U.S. patent application number 10/211596 was filed with the patent office on 2003-01-02 for fused abrasive particles, abrasive articles, and methods of making and using the same.
This patent application is currently assigned to 3M Innovative Properties Company. Invention is credited to Bange, Donna W., Celikkaya, Ahmet, Rosenflanz, Anatoly Z..
Application Number | 20030000151 10/211596 |
Document ID | / |
Family ID | 23970740 |
Filed Date | 2003-01-02 |
United States Patent
Application |
20030000151 |
Kind Code |
A1 |
Rosenflanz, Anatoly Z. ; et
al. |
January 2, 2003 |
Fused abrasive particles, abrasive articles, and methods of making
and using the same
Abstract
Fused abrasive particles comprising at least one eutectic. The
fused abrasive particles can be incorporated into abrasive products
such as coated abrasives, bonded abrasives, non-woven abrasives,
and abrasive brushes.
Inventors: |
Rosenflanz, Anatoly Z.;
(Maplewood, MN) ; Celikkaya, Ahmet; (Woodbury,
MN) ; Bange, Donna W.; (Eagan, MN) |
Correspondence
Address: |
Office of Intellectual Property Counsel
3M Innovative Properties Company
PO Box 33427
St. Paul
MN
55133-3427
US
|
Assignee: |
3M Innovative Properties
Company
|
Family ID: |
23970740 |
Appl. No.: |
10/211596 |
Filed: |
August 2, 2002 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
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10211596 |
Aug 2, 2002 |
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09619563 |
Jul 19, 2000 |
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6451077 |
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09619563 |
Jul 19, 2000 |
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09495978 |
Feb 2, 2000 |
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Current U.S.
Class: |
51/309 |
Current CPC
Class: |
C09K 3/1427 20130101;
B24D 3/14 20130101; C03C 14/004 20130101; C04B 35/117 20130101;
B24D 3/06 20130101; C04B 35/1115 20130101; C04B 35/653
20130101 |
Class at
Publication: |
51/309 |
International
Class: |
C09C 001/68; C09K
003/14 |
Claims
What is claimed is:
1. Fused, crystalline abrasive particles comprising at least one
eutectic, said eutectic comprising, on a theoretical oxide basis,
Al.sub.2O.sub.3 and at least one other metal oxide, wherein said
abrasive particles have a first average microhardness of at least
11 GPa, wherein said abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein said second average microhardness is at
least 85% of said first average microhardness.
2. The fused, crystalline abrasive particles according to claim 1
comprising at least 50 percent by volume, based on the total metal
oxide volume of the respective particle, of said eutectic.
3. The fused, crystalline abrasive particles according to claim 2
comprising, on a theoretical oxide basis, at least 40 percent by
weight Al.sub.2O.sub.3, based on the total metal oxide content the
respective particle.
4. The fused, crystalline abrasive particles according to claim 3,
wherein said second average microhardness is at least 90% of said
first average microhardness.
5. The fused, crystalline abrasive particles according to claim 4,
wherein said first average microhardness is at least 14 GPa.
6. The fused, crystalline abrasive particles according to claim 4,
wherein said first average microhardness is at least 16 GPa.
7. The fused, crystalline abrasive particles according to claim 4,
wherein said eutectic is Al.sub.2O.sub.3--Y.sub.3Al.sub.5O.sub.12
eutectic.
8. The fused, crystalline abrasive particles according to claim 4,
wherein said eutectic is selected from the group consisting of
Al.sub.2O.sub.3--Dy.sub.3Al.sub.5O.sub.12 eutectic,
Al.sub.2O.sub.3--Er.sub.3Al.sub.5O.sub.12 eutectic,
Al.sub.2O.sub.3--GdAlO.sub.3, eutectic and Al.sub.2O.sub.12
eutectic.
9. The fused, crystalline abrasive particles according to claim 4,
wherein said eutectic is selected from the group consisting of
CeAlO.sub.3--CeAl.sub.11O.sub.18 eutectic,
EuAlO.sub.3--EuAl.sub.11O.sub.- 18 eutectic,
LaAlO.sub.3--LaAl.sub.11O.sub.18 eutectic,
NdAlO.sub.3--NdAl.sub.11O.sub.18 eutectic,
PrAlO.sub.3--PrAl.sub.11O.sub.- 18 eutectic, and
SmAlO.sub.3--SmAl.sub.11O.sub.18 eutectic.
10. The fused, crystalline abrasive particles according to claim 4,
wherein said second average microhardness is at least 95% of said
first average microhardness.
11. Fused, crystalline abrasive particles comprising at least one
eutectic, the eutectic comprising ZrO.sub.2, on a theoretical oxide
basis, Al.sub.2O.sub.3, and at least one other metal oxide, wherein
the abrasive particles have a first average microhardness of at
least 11 GPa, wherein the abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein the second average microhardness is at
least 85% of the first average microhardness.
12. The fused, crystalline abrasive particles according to claim 11
comprising at least 50 percent by volume, based on the total metal
oxide volume of the respective particle, of said eutectic.
13. The fused, crystalline abrasive particles according to claim 12
comprising, on a theoretical oxide basis, at least 40 percent by
weight Al.sub.2O.sub.3, based on the total metal oxide content the
respective particle.
14. The fused, crystalline abrasive particles according to claim
13, wherein said second average microhardness is at least 90% of
said first average microhardness.
15. The fused, crystalline abrasive particles according to claim
14, wherein said first average microhardness is at least 14
GPa.
16. The fused, crystalline abrasive particles according to claim
14, wherein said first average microhardness is at least 16
GPa.
17. The fused, crystalline abrasive particles according to claim
14, wherein said eutectic is
Al.sub.2O.sub.3--Y.sub.3Al.sub.5O.sub.12--ZrO.su- b.2 eutectic.
18. The fused, crystalline abrasive particles according to claim
14, wherein said second average microhardness is at least 95% of
said first average microhardness.
19. Fused, crystalline abrasive particles comprising at least one
eutectic, the eutectic comprising at least (i) at least one of
crystalline, complex Al.sub.2O.sub.3.Y.sub.2O.sub.3 or crystalline,
complex Al.sub.2O.sub.3.REO and (ii) at least one of aluminoxy-D or
M-aluminoxy-D, wherein D is at least one of carbide or nitride, and
M is at least one metal cation other than Al, wherein said abrasive
particles have a first average microhardness of at least 11 GPa,
wherein said abrasive particles have a second average microhardness
after being heated in air at 1000.degree. C. in air for 4 hours,
and wherein said second average microhardness is at least 85% of
said first average microhardness.
20. The fused, crystalline abrasive particles according to claim 19
comprising at least 50 percent by volume, based on the total metal
oxide volume of the respective particle, of said eutectic.
21. The fused, crystalline abrasive particles according to claim 20
comprising, on a theoretical oxide basis, at least 40 percent by
weight Al.sub.2O.sub.3, based on the total metal oxide content the
respective particle.
22. The fused, crystalline abrasive particles according to claim
21, wherein said second average microhardness is at least 90% of
said first average microhardness.
23. The fused, crystalline abrasive particles according to claim
22, wherein said first average microhardness is at least 14
GPa.
24. Fused, crystalline abrasive particles comprising at least one
eutectic, the eutectic comprising at least (i) crystalline, complex
Al.sub.2O.sub.3.Y.sub.2O.sub.3 and (ii) at least one of aluminoxy-D
or M-aluminoxy-D, wherein D is at least one of carbide or nitride,
and M is at least one metal cation other than Al, wherein said
abrasive particles have a first average microhardness of at least
11 GPa, wherein said abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein said second average microhardness is at
least 85% of said first average microhardness.
25. The fused, crystalline abrasive particles according to claim 24
comprising at least 50 percent by volume, based on the total metal
oxide volume of the respective particle, of said eutectic.
26. The fused, crystalline abrasive particles according to claim 25
comprising, on a theoretical oxide basis, at least 40 percent by
weight Al.sub.2O.sub.3, based on the total metal oxide content the
respective particle.
27. The fused, crystalline abrasive particles according to claim
26, wherein said second average microhardness is at least 90% of
said first average microhardness.
28. The fused, crystalline abrasive particles according to claim
27, wherein said first average microhardness is at least 14
GPa.
29. A plurality of particles having a particle size distribution
ranging from fine to coarse, wherein at least a portion of said
plurality of particles are fused, crystalline abrasive particles
comprising at least one eutectic, said eutectic comprising, on a
theoretical oxide basis, Al.sub.2O.sub.3 and at least one other
metal oxide, wherein said abrasive particles have a first average
microhardness of at least 11 GPa, wherein the abrasive particles
have a second average microhardness after being heated in air at
1000.degree. C. in air for 4 hours, and wherein said second average
microhardness is at least 85% of said first average
microhardness.
30. A plurality of particles having a particle size distribution
ranging from fine to coarse, wherein at least a portion of said
plurality of particles are fused, crystalline abrasive particles
comprising at least one eutectic, said eutectic comprising
ZrO.sub.2, on a theoretical oxide basis, Al.sub.2O.sub.3, and at
least one other metal oxide, wherein said abrasive particles have a
first average microhardness of at least 11 GPa, wherein the
abrasive particles have a second average microhardness after being
heated in air at 1000.degree. C. in air for 4 hours, and wherein
said second average microhardness is at least 85% of said first
average microhardness.
31. A plurality of particles having a particle size distribution
ranging from fine to coarse, wherein at least a portion of said
plurality of particles are fused, crystalline abrasive particles
comprising at least (i) crystalline, complex Al.sub.2O.sub.3.REO
and (ii) at least one of aluminoxy-D or M-aluminoxy-D, wherein D is
at least one of carbide or nitride, and M is at least one metal
cation other than Al, wherein said abrasive particles have a first
average microhardness of at least 11 GPa, wherein the abrasive
particles have a second average microhardness after being heated in
air at 1000.degree. C. in air for 4 hours, and wherein said second
average microhardness is at least 85% of said first average
microhardness.
32. A plurality of particles having a particle size distribution
ranging from fine to coarse, wherein at least a portion of said
plurality of particles are fused, crystalline abrasive particles
comprising at least (i) crystalline, complex
Al.sub.2O.sub.3.Y.sub.2O.sub.3 and (ii) at least one of aluminoxy-D
or M-aluminoxy-D, wherein D is at least one of carbide or nitride,
and M is at least one metal cation other than Al, wherein said
abrasive particles have a first average microhardness of at least
11 GPa, wherein the abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein said second average microhardness is at
least 85% of said first average microhardness.
33. A plurality of abrasive particles having a specified nominal
grade, said plurality of abrasive particle having a particle size
distribution ranging from fine to coarse, wherein at least a
portion of said abrasive particles is a plurality of fused,
crystalline abrasive particles, said fused abrasive particles
comprising at least one eutectic, said eutectic comprising, on a
theoretical oxide basis, Al.sub.2O.sub.3 and at least one other
metal oxide, wherein said abrasive particles have a first average
microhardness of at least 11 GPa, wherein the abrasive particles
have a second average microhardness after being heated in air at
1000.degree. C. in air for 4 hours, and wherein said second average
microhardness is at least 85% of said first average
microhardness.
34. A plurality of abrasive particles having a specified nominal
grade, said plurality of abrasive particle having a particle size
distribution ranging from fine to coarse, wherein at least a
portion of said abrasive particles is a plurality of fused,
crystalline abrasive particles, said fused abrasive particles
comprising at least one eutectic, said eutectic comprising
ZrO.sub.2, on a theoretical oxide basis, Al.sub.2O.sub.3, and at
least one other metal oxide, wherein said abrasive particles have a
first average microhardness of at least 11 GPa, wherein the
abrasive particles have a second average microhardness after being
heated in air at 1000.degree. C. in air for 4 hours, and wherein
said second average microhardness is at least 85% of said first
average microhardness.
35. A plurality of abrasive particles having a specified nominal
grade, said plurality of abrasive particle having a particle size
distribution ranging from fine to coarse, wherein at least a
portion of said abrasive particles is a plurality of fused,
crystalline abrasive particles, said fused abrasive particles
comprising at least (i) crystalline, complex Al.sub.2O.sub.3.REO
and (ii) at least one of aluminoxy-D or M-aluminoxy-D, wherein D is
at least one of carbide or nitride, and M is at least one metal
cation other than Al, wherein said abrasive particles have a first
average microhardness of at least 11 GPa, wherein the abrasive
particles have a second average microhardness after being heated in
air at 1000.degree. C. in air for 4 hours, and wherein said second
average microhardness is at least 85% of said first average
microhardness.
36. A plurality of abrasive particles having a specified nominal
grade, said plurality of abrasive particle having a particle size
distribution ranging from fine to coarse, wherein at least a
portion of said abrasive particles is a plurality of fused,
crystalline abrasive particles, said fused abrasive particles
comprising at least (i) crystalline, complex
Al.sub.2O.sub.3.Y.sub.2O.sub.3 and (ii) at least one of aluminoxy-D
or M-aluminoxy-D, wherein D is at least one of carbide or nitride,
and M is at least one metal cation other than Al, wherein said
abrasive particles have a first average microhardness of at least
11 GPa, wherein the abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein said second average microhardness is at
least 85% of said first average microhardness.
37. A method for making fused, crystalline abrasive particles
comprising at least one eutectic, said eutectic comprising, on a
theoretical oxide basis, Al.sub.2O.sub.3 and at least one other
metal oxide, wherein the abrasive particles have a first average
microhardness of at least 11 GPa, wherein the abrasive particles
have a second average microhardness after being heated in air at
1000.degree. C. in air for 4 hours, and wherein said second average
microhardness is at least 85% of said first average microhardness,
said method comprising: melting at least one Al.sub.2O.sub.3 source
and at least one reactive Al.sub.2O.sub.3 metal oxide source to
provide a melt; and converting the melt to said fused, crystalline
abrasive particles.
38. The method according to claim 37, wherein converting includes:
cooling the melt to provide a solidified material; and crushing the
solidified material to provide said fused, crystalline abrasive
particles.
39. The method according to claim 38, wherein cooling the melt
includes cooling the melt with metallic plates.
40. The method according to claim 38, wherein cooling the melt
includes cooling the melt with metallic balls.
41. A method for making fused, crystalline abrasive particles
comprising at least one eutectic, said eutectic comprising
ZrO.sub.2, on a theoretical oxide basis, Al.sub.2O.sub.3, and at
least one other metal oxide, wherein the abrasive particles have a
first average microhardness of at least 11 GPa, wherein the
abrasive particles have a second average microhardness after being
heated in air at 1000.degree. C. in air for 4 hours, and wherein
said second average microhardness is at least 85% of said first
average microhardness, said method comprising: melting at least one
Al.sub.2O.sub.3 source and at least one reactive Al.sub.2O.sub.3
metal oxide source to provide a melt; and converting the melt to
said fused, crystalline abrasive particles.
42. An abrasive article comprising a binder and a plurality of
abrasive particles, wherein at least a portion of said abrasive
particles are fused, crystalline abrasive particles comprising at
least one eutectic, said eutectic comprising, on a theoretical
oxide basis, Al.sub.2O.sub.3 and at least one other metal oxide,
wherein said abrasive particles have a first average microhardness
of at least 11 GPa, wherein the abrasive particles have a second
average microhardness after being heated in air at 1000.degree. C.
in air for 4 hours, and wherein said second average microhardness
is at least 85% of said first average microhardness.
43. The abrasive article according to claim 42, wherein said
article is a coated abrasive article, and further comprises a
backing.
44. The abrasive article according to claim 42, wherein said
article is a bonded abrasive article.
45. The abrasive article according to claim 42, wherein said
article is a nonwoven abrasive article, and further comprises a
nonwoven web.
46. An abrasive article comprising a binder and a plurality of
abrasive particles, wherein at least a portion of said abrasive
particles are fused, crystalline abrasive particles comprising at
least one eutectic, said eutectic comprising ZrO.sub.2, on a
theoretical oxide basis, Al.sub.2O.sub.3, and at least one other
metal oxide, wherein said abrasive particles have a first average
microhardness of at least 11 GPa, wherein the abrasive particles
have a second average microhardness after being heated in air at
1000.degree. C. in air for 4 hours, and wherein said second average
microhardness is at least 85% of said first average
microhardness.
47. An abrasive article comprising a binder and a plurality of
abrasive particles, wherein at least a portion of said abrasive
particles are fused, crystalline abrasive particles comprising at
least one eutectic, said eutectic comprising at least (i)
crystalline, complex Al.sub.2O.sub.3.REO and (ii) at least one of
aluminoxy-D or M-aluminoxy-D, wherein D is at least one of carbide
or nitride, and M is at least one metal cation other than Al,
wherein said abrasive particles have a first average microhardness
of at least 11 GPa, wherein the abrasive particles have a second
average microhardness after being heated in air at 1000.degree. C.
in air for 4 hours, and wherein said second average microhardness
is at least 85% of said first average microhardness.
48. An abrasive article comprising a binder and a plurality of
abrasive particles, wherein at least a portion of said abrasive
particles are fused, crystalline abrasive particles comprising at
least one eutectic, said eutectic comprising at least (i)
crystalline, complex Al.sub.2O.sub.3.Y.sub.2O.sub.3 and (ii) at
least one of aluminoxy-D or M-aluminoxy-D, wherein D is at least
one of carbide or nitride, and M is at least one metal cation other
than Al, wherein said abrasive particles have a first average
microhardness of at least 11 GPa, wherein the abrasive particles
have a second average microhardness after being heated in air at
1000.degree. C. in air for 4 hours, and wherein said second average
microhardness is at least 85% of said first average
microhardness.
49. A vitrified bonded abrasive article comprising a plurality of
abrasive particles bonded together via vitrified bonding material,
wherein at least a portion of said plurality of abrasive particles
are fused, crystalline abrasive particles comprising at least one
eutectic, said eutectic comprising, on a theoretical oxide basis,
Al.sub.2O.sub.3 and at least one other metal oxide, wherein said
abrasive particles have a first average microhardness of at least
11 GPa, wherein the abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein said second average microhardness is at
least 85% of said first average microhardness.
50. The vitrified bonded abrasive article according to claim 49,
wherein said vitrified bonding material comprises silica, alumina,
and boria.
51. The vitrified bonded abrasive article according to claim 50,
wherein said vitrified bonding material comprises at least 10
percent by weight of said alumina.
52. The vitrified bonded abrasive article according to claim 51,
wherein said vitrified bonding material comprises at least 10
percent by weight of said boria.
53. A vitrified bonded abrasive article comprising a plurality of
abrasive particles bonded together via vitrified bonding material,
wherein at least a portion of said plurality of abrasive particles
are fused, crystalline abrasive particles comprising at least one
eutectic, said eutectic comprising ZrO.sub.2, on a theoretical
oxide basis, Al.sub.2O.sub.3, and at least one other metal oxide,
wherein said abrasive particles have a first average microhardness
of at least 11 GPa, wherein the abrasive particles have a second
average microhardness after being heated in air at 1000.degree. C.
in air for 4 hours, and wherein said second average microhardness
is at least 85% of said first average microhardness.
54. A vitrified bonded abrasive article comprising a plurality of
abrasive particles bonded together via vitrified bonding material,
wherein at least a portion of said plurality of abrasive particles
are fused, crystalline abrasive particles comprising at least (i)
crystalline, complex Al.sub.2O.sub.3.REO and (ii) at least one of
aluminoxy-D or M-aluminoxy-D, wherein D is at least one of carbide
or nitride, and M is at least one metal cation other than Al,
wherein said abrasive particles have a first average microhardness
of at least 11 GPa, wherein the abrasive particles have a second
average microhardness after being heated in air at 1000.degree. C.
in air for 4 hours, and wherein said second average microhardness
is at least 85% of said first average microhardness.
55. A vitrified bonded abrasive article comprising a plurality of
abrasive particles bonded together via vitrified bonding material,
wherein at least a portion of said plurality of abrasive particles
are fused, crystalline abrasive particles comprising at least (i)
crystalline, complex Al.sub.2O.sub.3.Y.sub.2O.sub.3 and (ii) at
least one of aluminoxy-D or M-aluminoxy-D, wherein D is at least
one of carbide or nitride, and M is at least one metal cation other
than Al, wherein said abrasive particles have a first average
microhardness of at least 11 GPa, wherein the abrasive particles
have a second average microhardness after being heated in air at
1000.degree. C. in air for 4 hours, and wherein said second average
microhardness is at least 85% of said first average
microhardness.
56. A method of abrading a surface comprising: contacting a
plurality of abrasive particles comprising at least one eutectic,
said eutectic comprising, on a theoretical oxide basis,
Al.sub.2O.sub.3 and at least one other metal oxide with a surface
of a workpiece, wherein said abrasive particles have a first
average microhardness of at least 11 GPa, wherein the abrasive
particles have a second average microhardness after being heated in
air at 1000.degree. C. in air for 4 hours, and wherein said second
average microhardness is at least 85% of said first average
microhardness; and moving at least one of said plurality of
abrasive particles or said surface relative to the other to abrade
at least a portion of said surface with at least one of said fused
abrasive particles.
57. A method of abrading a surface comprising: contacting a
plurality of abrasive particles comprising at least one eutectic,
said eutectic comprising ZrO.sub.2, on a theoretical oxide basis,
Al.sub.2O.sub.3, and at least one other metal oxide with a surface
of a workpiece, wherein said abrasive particles have a first
average microhardness of at least 11 GPa, wherein the abrasive
particles have a second average microhardness after being heated in
air at 1000.degree. C. in air for 4 hours, and wherein said second
average microhardness is at least 85% of said first average
microhardness; and moving at least one of said plurality of
abrasive particles or said surface relative to the other to abrade
at least a portion of said surface with at least one of said fused
abrasive particles.
58. A method of abrading a surface comprising: contacting a
plurality of abrasive particles comprising at least one eutectic,
said eutectic comprising at least (i) crystalline, complex
Al.sub.2O.sub.3.REO and (ii) at least one of aluminoxy-D or
M-aluminoxy-D, wherein D is at least one of carbide or nitride, and
M is at least one metal cation other than Al with a surface of a
workpiece, wherein said abrasive particles have a first average
microhardness of at least 11 GPa, wherein the abrasive particles
have a second average microhardness after being heated in air at
1000.degree. C. in air for 4 hours, and wherein said second average
microhardness is at least 85% of said first average microhardness;
and moving at least one of said plurality of abrasive particles or
said surface relative to the other to abrade at least a portion of
said surface with at least one of said fused abrasive
particles.
59. A method of abrading a surface comprising: contacting a
plurality of abrasive particles comprising at least one eutectic,
said eutectic comprising at least (i) crystalline, complex
Al.sub.2O.sub.3.Y.sub.2O.sub- .3 and (ii) at least one of
aluminoxy-D or M-aluminoxy-D, wherein D is at least one of carbide
or nitride, and M is at least one metal cation other than Al with a
surface of a workpiece, wherein said abrasive particles have a
first average microhardness of at least 11 GPa, wherein the
abrasive particles have a second average microhardness after being
heated in air at 1000.degree. C. in air for 4 hours, and wherein
said second average microhardness is at least 85% of said first
average microhardness; and moving at least one of said plurality of
abrasive particles or said surface relative to the other to abrade
at least a portion of said surface with at least one of said fused
abrasive particles.
Description
[0001] This is a continuation-in-part of U.S. Ser. No. 09/495,978,
filed Feb. 2, 2000, the disclosure of which is incorporated herein
by reference.
FIELD OF THE INVENTION
[0002] This invention pertains to fused abrasive particles and
methods of making the same. The fused abrasive particles can be
incorporated into a variety of abrasive articles, including bonded
abrasives, coated abrasives, nonwoven abrasives, and abrasive
brushes.
DESCRIPTION OF RELATED ART
[0003] There are a variety of abrasive particles (e.g., diamond
particles, cubic boron nitride particles, fused abrasive particles,
and sintered, ceramic abrasive particles (including sol-gel-derived
abrasive particles) known in the art. In some abrading
applications, the abrasive particles are used in loose form, while
in others the particles are incorporated into abrasive products
(e.g., coated abrasive products, bonded abrasive products,
non-woven abrasive products, and abrasive brushes). Criteria used
in selecting abrasive particles used for a particular abrading
application include: abrading life, rate of cut, substrate surface
finish, grinding efficiency, and product cost.
[0004] From about 1900 to about the mid-1980's, the premier
abrasive particles for abrading applications such as those
utilizing coated and bonded abrasive products were typically fused
abrasive particles. There are two general types of fused abrasive
particles: (1) fused alpha alumina abrasive particles (see, e.g.,
U.S. Pat. Nos. 1,161,620 (Coulter), 1,192,709 (Tone), 1,247,337
(Saunders et al.), 1,268,533 (Allen), and 2,424,645 (Baumann et
al.)) and (2) fused (sometimes also referred to as "co-fused")
alumina-zirconia abrasive particles (see, e.g., U.S. Pat. Nos.
3,891,408 (Rowse et al.), 3,781,172 (Pett et al.), 3,893,826
(Quinan et al.), 4,126,429 (Watson), 4,457,767 (Poon et al.), and
5,143,522 (Gibson et al.))(also see, e.g., U.S. Pat. Nos. 5,023,212
(Dubots et. al) and 5,336,280 (Dubots et. al) which report the
certain fused oxynitride abrasive particles). Fused alumina
abrasive particles are typically made by charging a furnace with an
alumina source such as aluminum ore or bauxite, as well as other
desired additives, heating the material above its melting point,
cooling the melt to provide a solidified mass, crushing the
solidified mass into particles, and then screening and grading the
particles to provide the desired abrasive particle size
distribution. Fused alumina-zirconia abrasive particles are
typically made in a similar manner, except the furnace is charged
with both an alumina source and a zirconia source, and the melt is
more rapidly cooled than the melt used to make fused alumina
abrasive particles. For fused alumina-zirconia abrasive particles,
the amount of alumina source is typically about 50-80 percent by
weight, and the amount of zirconia, 50-20 percent by weight
zirconia. The processes for making the fused alumina and fused
alumina abrasive particles may include removal of impurities from
the melt prior to the cooling step.
[0005] Although fused alpha alumina abrasive particles and fused
alumina-zirconia abrasive particles are still widely used in
abrading applications (including those utilizing coated and bonded
abrasive products, the premier abrasive particles for many abrading
applications since about the mid-1980's are sol-gel-derived alpha
alumina particles (see, e.g., U.S. Pat. Nos. 4,314,827 (Leitheiser
et al.), 4,518,397 (Leitheiser et al.), 4,623,364 (Cottringer et
al.), 4,744,802 (Schwabel), 4,770,671 (Monroe et al.), 4,881,951
(Wood et al.), 4,960,441 (Pellow et al.), 5,139,978 (Wood),
5,201,916 (Berg et al.), 5,366,523 (Rowenhorst et al.), 5,429,647
(Larmie), 5,547,479 (Conwell et al.), 5,498,269 (Larmie), 5,551,963
(Larmie), and 5,725,162 (Garg et al.)).
[0006] The sol-gel-derived alpha alumina abrasive particles may
have a microstructure made up of very fine alpha alumina
crystallites, with or without the presence of secondary phases
added. The grinding performance of the sol-gel derived abrasive
particles on metal, as measured, for example, by life of abrasive
products made with the abrasive particles was dramatically longer
than such products made from conventional fused alumina abrasive
particles.
[0007] Typically, the processes for making sol-gel-derived abrasive
particles are more complicated and expensive than the processes for
making conventional fused abrasive particles. In general,
sol-gel-derived abrasive particles are typically made by preparing
a dispersion or sol comprising water, alumina monohydrate
(boehmite), and optionally peptizing agent (e.g., an acid such as
nitric acid), gelling the dispersion, drying the gelled dispersion,
crushing the dried dispersion into particles, screening the
particles to provide the desired sized particles, calcining the
particles to remove volatiles, sintering the calcined particles at
a temperature below the melting point of alumina, and screening and
grading the particles to provide the desired abrasive particle size
distribution. Frequently a metal oxide modifier(s) is incorporated
into the sintered abrasive particles to alter or otherwise modify
the physical properties and/or microstructure of the sintered
abrasive particles.
[0008] There are a variety of abrasive products (also referred to
"abrasive articles") known in the art. Typically, abrasive products
include binder and abrasive particles secured within the abrasive
product by the binder. Examples of abrasive products include:
coated abrasive products, bonded abrasive products, nonwoven
abrasive products, and abrasive brushes.
[0009] Examples of bonded abrasive products include: grinding
wheels, cutoff wheels, and honing stones). The main types of
bonding systems used to make bonded abrasive products are:
resinoid, vitrified, and metal. Resinoid bonded abrasives utilize
an organic binder system (e.g., phenolic binder systems) to bond
the abrasive particles together to form the shaped mass (see, e.g.,
U.S. Pat. Nos. 4,741,743 (Narayanan et al.), 4,800,685 (Haynes et
al.), 5,038,453 (Narayanan et al.), and 5,110,332 (Narayanan et
al.)). Another major type are vitrified wheels in which a glass
binder system is used to bond the abrasive particles together mass
(see, e.g., U.S. Pat. Nos. 4,543,107 (Rue), 4,898,587 (Hay et al.),
4,997,461 (Markhoff-Matheny et al.), and 5,863,308 (Qi et al.)).
These glass bonds are usually matured at temperatures between
900.degree. C. to 1300.degree. C. Today vitrified wheels utilize
both fused alumina and sol-gel-derived abrasive particles. However,
fused alumina-zirconia is generally not incorporated into vitrified
wheels due in part to the thermal stability of alumina-zirconia. At
the elevated temperatures at which the glass bonds are matured, the
physical properties of alumina-zirconia degrade, leading to a
significant decrease in their abrading performance. Metal bonded
abrasive products typically utilize sintered or plated metal to
bond the abrasive particles.
[0010] The abrasive industry continues to desire abrasive particles
and abrasive products that are easier to make, cheaper to make,
and/or provide performance advantage(s) over conventional abrasive
particles and products.
SUMMARY OF THE INVENTION
[0011] The present invention provides fused, crystalline abrasive
particles comprising at least one eutectic, the eutectic
comprising, on a theoretical oxide basis, Al.sub.2O.sub.3 and at
least one other metal oxide, wherein the abrasive particles have a
first average microhardness of at least 11 GPa (preferably, at
least 12, 13, or 14 GPa, more preferably, at least 15 GPa, and even
more preferably, at least 16 GPa, at least 17 GPa, or even at least
18 GPa), wherein the abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein the second average microhardness is at
least 85% (preferably, at least 90%; more preferably, at least 95%;
and even more preferably, at least 100%) of the first average
microhardness.
[0012] Preferred embodiments according to the present invention
include fused, crystalline abrasive particles comprising at least
one eutectic, the eutectic comprising ZrO.sub.2, on a theoretical
oxide basis, Al.sub.2O.sub.3, and at least one other metal oxide,
wherein the abrasive particles have a first average microhardness
of at least 11 GPa (preferably, at least 12, 13, or 14 GPa, more
preferably, at least 15 GPa, and even more preferably, at least 16
GPa, at least 17 GPa, or even at least 18 GPa), wherein the
abrasive particles have a second average microhardness after being
heated in air at 1000.degree. C. in air for 4 hours, and wherein
the second average microhardness is at least 85% (preferably, at
least 90%; more preferably, at least 95%; and even more preferably,
at least 100%) of the first average microhardness.
[0013] Preferred embodiments according to the present invention
also include fused, crystalline abrasive particles comprising at
least one eutectic, the eutectic comprising at least (i)
crystalline, complex Al.sub.2O.sub.3.REO and (ii) at least one of
aluminoxy-D or M-aluminoxy-D, wherein D is at least one of carbide
or nitride, and M is at least one metal cation other than Al,
wherein the abrasive particles have a first average microhardness
of at least 11 GPa (preferably, at least 12, 13, or 14 GPa, more
preferably, at least 15 GPa, and even more preferably, at least 16
GPa), wherein the abrasive particles have a second average
microhardness after being heated in air at 1000.degree. C. in air
for 4 hours, and wherein the second average microhardness is at
least 85% (preferably, at least 90%; more preferably, at least 95%;
and even more preferably, at least 100%) of the first average
microhardness.
[0014] Preferred embodiments according to the present invention
also include fused, crystalline abrasive particles comprising at
least one eutectic, the eutectic comprising at least (i)
crystalline, complex Al.sub.2O.sub.3.Y.sub.2O.sub.3 and (ii) at
least one of aluminoxy-D or M-aluminoxy-D, wherein D is at least
one of carbide or nitride, and M is at least one metal cation other
than Al, wherein the abrasive particles have a first average
microhardness of at least 11 GPa (preferably, at least 12, 13, or
14 GPa, more preferably, at least 15 GPa, and even more preferably,
at least 16 GPa), wherein the abrasive particles have a second
average microhardness after being heated in air at 1000.degree. C.
in air for 4 hours, and wherein the second average microhardness is
at least 85% (preferably, at least 90%; more preferably, at least
95%; and even more preferably, at least 100%) of the first average
microhardness.
[0015] Preferably, fused, crystalline abrasive particles according
to the present invention comprise at least 20, 30, 40, 50, 60, 70,
75, 80, 85, 90, 95, 98, 99, or even 100 percent of the eutectic(s)
by volume, based on the total metal oxide, carbide, and/or nitride
content, as the case may be, volume of the respective particle. In
another aspect, fused, crystalline abrasive particles according to
the present invention preferably comprises, on a theoretical oxide
basis, at least 30 percent (or even at least 40, 50, 60, 70, or 80
percent) by weight Al.sub.2O.sub.3, based on the total metal oxide,
carbide, and/or nitride content, as the case may be, content the
respective particle.
[0016] In another aspect, the present invention provides a
plurality of particles having a particle size distribution ranging
from fine to coarse, wherein at least a portion of the plurality of
particles are fused, crystalline abrasive particles according to
the present invention.
[0017] One method for making fused, crystalline abrasive particles
according to the present invention, the method comprises:
[0018] melting at least one Al.sub.2O.sub.3 source and at least one
other metal oxide source (typically, at least one reactive
Al.sub.2O.sub.3 metal oxide source) to provide a melt; and
[0019] converting the melt to fused, crystalline abrasive particles
according to the present invention.
[0020] In another method for making fused, crystalline abrasive
particles according to the present invention, the method
comprises:
[0021] melting at least one Al.sub.2O.sub.3 source and at least one
Y.sub.2O.sub.3 source to provide a melt, wherein and at least one
source of nitrogen (e.g. AIN) or carbon (e.g. Al.sub.4C.sub.3) is
provided in the melt; and
[0022] converting the melt to the fused, crystalline abrasive
particles.
[0023] In another method for making fused, crystalline abrasive
particles according to the present invention, the method
comprises:
[0024] melting at least one Al.sub.2O.sub.3 source and at least one
REO source to provide a melt, wherein and at least one source of
nitrogen (e.g. AIN) or carbon (e.g. Al.sub.4C.sub.3) is provided in
the melt; and
[0025] converting the melt to the fused, crystalline abrasive
particles.
[0026] In this application:
[0027] "simple metal oxide" refers to a metal oxide comprised of a
one or more of the same metal element and oxygen (e.g.,
Al.sub.2O.sub.3, CeO.sub.2, MgO, SiO.sub.2, and
Y.sub.2O.sub.3);
[0028] "complex metal oxide" refers to a metal oxide comprised of
two or more different metal elements and oxygen (e.g.,
CeAl.sub.11O.sub.18, Dy.sub.3Al.sub.5O.sub.12, MgAl.sub.2O.sub.4,
and Y.sub.3Al.sub.5O.sub.12)- ;
[0029] "complex Al.sub.2O.sub.3 .metal oxide" refers to a complex
metal oxide comprised of, on a theoretical oxide basis,
Al.sub.2O.sub.3 and one or more metal elements other than Al (e.g.,
CeAl.sub.11O.sub.18, Dy.sub.3Al.sub.5O.sub.12, MgAl.sub.2O.sub.4,
and Y.sub.3Al.sub.5O.sub.12)- ;
[0030] "complex Al.sub.2O.sub.3.Y.sub.2O.sub.3" refers to a complex
metal oxide comprised of, on a theoretical oxide basis,
Al.sub.2O.sub.3 and Y.sub.2O.sub.3 (e.g.,
Y.sub.3Al.sub.5O.sub.12);
[0031] "complex Al.sub.2O.sub.3.rare earth oxide" refers to a
complex metal oxide comprised of, on a theoretical oxide basis,
Al.sub.2O.sub.3 and rare earth oxide (e.g., CeAl.sub.11O.sub.18 and
Dy.sub.3Al.sub.5O.sub.12);
[0032] "reactive Al.sub.2O.sub.3 metal oxide" refers to a metal
oxide other than Al.sub.2O.sub.3 (e.g., Dy.sub.2O.sub.3 or
Y.sub.2O.sub.3) that can react with Al.sub.2O.sub.3 to form at
least one complex Al.sub.2O.sub.3 .metal oxide;
[0033] "rare earth oxides" refer to, on a theoretical oxide basis,
CeO.sub.2, Dy.sub.2O.sub.3, Er.sub.2O.sub.3, Eu.sub.2O.sub.3,
Gd.sub.2O.sub.3, Ho.sub.2O.sub.3, La.sub.2O.sub.3, Lu.sub.2O.sub.3,
Nd.sub.2O.sub.3, Pr.sub.6O.sub.11, Sm.sub.2O.sub.3,
Th.sub.4O.sub.7, Tm.sub.2O.sub.3, and Yb.sub.2O.sub.3;
[0034] "REO" means rare earth oxide; and
[0035] "particle size" is the longest dimension of a particle.
[0036] Fused abrasive particles according to the present invention
can be incorporated into various abrasive products such as coated
abrasives, bonded abrasives, nonwoven abrasives, and abrasive
brushes.
[0037] The present invention also provides a method of abrading a
surface, the method comprising:
[0038] contacting fused abrasive particles according to the present
invention with a surface of a workpiece; and
[0039] moving at least one of the fused abrasive particles
according to the present invention or the surface relative to the
other to abrade at least a portion of the surface with at least one
of the fused abrasive particles according to the present
invention.
[0040] Preferred fused abrasive particles according to the present
invention provide superior grinding performance as compared to
current fused abrasive particles. Preferred fused abrasive
particles according to the present invention are sufficiently
microstructurally and chemically stable to allow them to be used
with vitrified bonding systems without the significant decrease in
abrading performance of conventional alumina-zirconia abrasive
particles used with vitrified bonding systems.
BRIEF DESCRIPTION OF THE DRAWINGS
[0041] FIG. 1 is a fragmentary cross-sectional schematic view of a
coated abrasive article including fused abrasive particles
according to the present invention;
[0042] FIG. 2 is a perspective view of a bonded abrasive article
including fused abrasive particles according to the present
invention;
[0043] FIG. 3 is an enlarged schematic view of a nonwoven abrasive
article including fused abrasive particles according to the present
invention;
[0044] FIG. 4 is a schematic of an exemplary portion of
interpenetrating phases in a eutectic colony;
[0045] FIG. 5 is a Differential thermal analysis (DTA) plot and
Thermogravimetric Analysis (TGA) plot of Example 1 fused
material;
[0046] FIG. 6 is a DTA plot and TGA plot of Comparative Example D
fused material;
[0047] FIG. 7 is a DTA plot and TGA plot of Comparative Example B
abrasive particles;
[0048] FIGS. 8 and 9 are scanning electron photomicrographs of
polished cross-sections of Examples 1 and 2 fused material,
respectively;
[0049] FIGS. 10 and 11 are scanning electron photomicrographs of
polished cross-sections of Comparative Examples D and B fused
material, respectively;
[0050] FIGS. 12-14 are scanning electron photomicrographs of
polished cross-sections of Comparative Example B abrasive particles
after exposure to various heating conditions;
[0051] FIG. 15 is a scanning electron photomicrograph of a polished
cross-section of Comparative Example D fused material;
[0052] FIG. 16 is a scanning electron photomicrographs of polished
cross-section of Comparative Example D abrasive particle after
exposure to a specified heating condition;
[0053] FIGS. 17 and 18 are scanning electron photomicrographs of
polished cross-section of Example 3 abrasive particles;
[0054] FIGS. 19-30 are scanning electron photomicrographs of
polished cross-sections of Example 4-15 abrasive particles,
respectively;
[0055] FIG. 31 is a DTA plot and TGA plot of Example 10 abrasive
particles; and
[0056] FIGS. 32-49 are scanning electron photomicrographs of
polished cross-sections of Example 16-33 fused material,
respectively.
DETAILED DESCRIPTION
[0057] Fused Abrasive particles according to the present invention
can be made by heating the appropriate metal oxides sources to form
a melt, preferably a homogenous melt, and then rapidly cooling the
melt to provide a solidified mass. The solidified mass is typically
crushed to produce the desired particle size distribution of
abrasive particles.
[0058] More specifically, fused abrasive particles according to the
present invention can be made by charging a furnace with sources of
the appropriate raw materials (e.g., depending on the composition
of the fused abrasive particles, materials such as metal oxide(s),
metal carbides, metal nitrides, metal oxycaribides, and/or metal
oxynitrides), and other optional additives (e.g., other metal
carbides, nitrides, oxides, metal borides, and processing aids).
The raw materials can be added to the furnace, for example,
together and melted, or sequentially and melted.
[0059] For solidified melt material containing complex metal
oxide(s), at least a portion of the metal oxide present in the
melted metal oxide sources (i.e., the melt) react to form complex
metal oxide(s) during formation process of the solidified material.
For example, an Al.sub.2O.sub.3 source and a Y.sub.2O.sub.3 source
may react to form Y.sub.3Al.sub.5O.sub.12 (i.e.,
5Al.sub.2O.sub.3+3Y.sub.2O.sub.3.fwdarw.2Y- .sub.3Al.sub.5O.sub.12,
or YAlO.sub.3 (i.e., Al.sub.2O.sub.3+Y.sub.2O.sub.-
3.fwdarw.2YAlO.sub.3), or Y.sub.4Al.sub.2O.sub.9 (i.e.,
Al.sub.2O.sub.3+2Y.sub.2O.sub.3.fwdarw.Y.sub.4Al.sub.2O.sub.9).
Similarly, for example, an Al.sub.2O.sub.3 source and an
Er.sub.2O.sub.3 or a Yb.sub.2O.sub.3 source may react to form
Er.sub.3Al.sub.5O.sub.12 and Yb.sub.3Al.sub.5O.sub.12,
respectively. Further, for example, an Al.sub.2O.sub.3 source and a
Gd.sub.2O.sub.3 source may react to form GdAlO.sub.3 (i.e.,
Al.sub.2O.sub.3+Gd.sub.2O.sub.3.fwdarw.2GdAlO.sub.3). Similarly,
for example, an Al.sub.2O.sub.3 source and a CeO.sub.2,
Dy.sub.2O.sub.3, Eu.sub.2O.sub.3, La.sub.2O.sub.3, Nd.sub.2O.sub.3,
Pr.sub.2O.sub.3, or Sm.sub.2O.sub.3 source may react to form
CeAlO.sub.3, Dy.sub.3Al.sub.5O.sub.12, EuAlO.sub.3, LaAlO.sub.3,
NdAlO.sub.3, PrAlO.sub.3, and SmAlO.sub.3, respectively. Further,
for example, an Al.sub.2O.sub.3 source and a La.sub.2O.sub.3 source
may react to form LaAlO.sub.3 (i.e.,
Al.sub.2O.sub.3+La.sub.2O.sub.3.fwdarw.2LaAlO.sub.3) and
LaAl.sub.11O.sub.18 (i.e.,
11Al.sub.2O.sub.3+La.sub.2O.sub.3.fwdarw.2- LaAl.sub.11O.sub.18).
Similarly, for example, an Al.sub.2O.sub.3 source and CeO.sub.2,
Eu.sub.2O.sub.3, Nd.sub.2O.sub.3, Pr.sub.2O.sub.3, or
Sm.sub.2O.sub.3 source may react to form CeAlO.sub.11O.sub.18,
EuAl.sub.11O.sub.18, NdAl.sub.11O.sub.18, PrAl.sub.11O.sub.18, and
SMAl.sub.11O.sub.18, respectively.
[0060] Depending upon the relative proportions of Al.sub.2O.sub.3
and Y.sub.2O.sub.3 or rare earth oxide, the resultant solidified
material, and ultimately the fused abrasive particles,
comprises:
[0061] (a) crystalline Al.sub.2O.sub.3 together with crystalline
Al.sub.2O.sub.3-complex Al.sub.2O.sub.3.metal oxide (complex
Al.sub.2O.sub.3.metal oxide is, for example,
Y.sub.3Al.sub.5O.sub.12, Dy.sub.3Al.sub.5O.sub.12,
Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or Yb.sub.3Al.sub.5O.sub.12)
eutectic;
[0062] (b) Al.sub.2O.sub.3-complex Al.sub.2O.sub.3.metal oxide
(again complex Al.sub.2O.sub.3.metal oxide is, for example,
Y.sub.3Al.sub.5O.sub.12, Dy.sub.3Al.sub.5O.sub.12,
Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or Yb.sub.3Al.sub.5O.sub.12)
eutectic; and/or
[0063] (c) crystalline complex Al.sub.2O.sub.3.metal oxide (again,
complex Al.sub.2O.sub.3.metal oxide is, for example,
Y.sub.3Al.sub.5O.sub.12, Dy.sub.3Al.sub.5O.sub.12,
Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or Yb.sub.3A.sub.5O.sub.12)
together with crystalline Al.sub.2O.sub.3-complex
Al.sub.2O.sub.3.metal oxide (again complex Al.sub.2O.sub.3.metal
oxide is, for example, Y.sub.3Al.sub.5O.sub.12,
Dy.sub.3Al.sub.5O.sub.12, Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or
Yb.sub.3Al.sub.5O.sub.12) eutectic.
[0064] If Al.sub.2O.sub.3 reacts with Y.sub.2O.sub.3 to form two
complex metal oxides, the resulting solidified material, and
ultimately the fused abrasive particles, depending upon the
relative proportions of Al.sub.2O.sub.3 and Y.sub.2O.sub.3,
comprises:
[0065] (a) first crystalline complex Al.sub.2O.sub.3.metal oxide
(e.g., Y.sub.3Al.sub.5O.sub.12 or YAlO.sub.3) together with first
crystalline complex Al.sub.2O.sub.3.metal oxide (again, e.g.,
Y.sub.3Al.sub.5O.sub.12 or YAlO.sub.3, respectively)-second,
different, crystalline complex Al.sub.2O.sub.3.metal oxide (e.g.,
YAlO.sub.3 or Y.sub.4Al.sub.2O.sub.9, respectively) eutectic;
[0066] (b) first crystalline complex Al.sub.2O.sub.3.metal oxide
(again, e.g., Y.sub.3Al.sub.5O.sub.12 or YAlO.sub.3)-second,
different, crystalline complex Al.sub.2O.sub.3.metal oxide (again,
e.g., YAlO.sub.3 or Y.sub.4Al.sub.2O.sub.9, respectively) eutectic;
and/or
[0067] (c) second, different, crystalline complex
Al.sub.2O.sub.3.metal oxide (again, e.g., YAlO.sub.3 or
Y.sub.4Al.sub.2O.sub.9) together with first crystalline complex
Al.sub.2O.sub.3.metal oxide (again, e.g., Y.sub.3Al.sub.5O.sub.12
or YAlO.sub.3)-second, different, crystalline complex
Al.sub.2O.sub.3.metal oxide (again, e.g., YAlO.sub.3 or
Y.sub.4Al.sub.2O.sub.9, respectively) eutectic.
[0068] If Al.sub.2O.sub.3 reacts with rare earth oxide to form two
complex metal oxides, the resulting solidified material, and
ultimately the fused abrasive particles, depending upon the
relative proportions of Al.sub.2O.sub.3 and rare earth oxide,
comprises:
[0069] (a) first crystalline complex Al.sub.2O.sub.3.metal oxide
(e.g., CeAlO.sub.3, EuAlO.sub.3, LaAlO.sub.3, NdAlO.sub.3,
PrAlO.sub.3, or SmAlO.sub.3) together with first crystalline
complex Al.sub.2O.sub.3.metal oxide (again, e.g., CeAlO.sub.3,
EuAlO.sub.3, LaAlO.sub.3, NdAlO.sub.3, PrAlO.sub.3, or
SmAlO.sub.3)-second, different, crystalline complex
Al.sub.2O.sub.3.metal oxide (e.g., CeAl.sub.11O.sub.18,
EuAl.sub.11O.sub.18, LaAl.sub.11O.sub.18, NdAl.sub.11O.sub.18;
PrAl.sub.11O.sub.18, or SmAl.sub.11O.sub.18, respectively)
eutectic;
[0070] (b) first crystalline complex Al.sub.2O.sub.3.metal oxide
(again, e.g., CeAlO.sub.3, EuAlO.sub.3, LaAlO.sub.3, NdAlO.sub.3,
PrAlO.sub.3, or SmAlO.sub.3)-second, different, crystalline complex
Al.sub.2O.sub.3.metal oxide (again, e.g., CeAl.sub.11O.sub.18,
EuAl.sub.11O.sub.18, LaAl.sub.11O.sub.18, NdAl.sub.11O.sub.18,
PrAl.sub.11O.sub.18, or SmAl.sub.11O.sub.18, respectively)
eutectic; and/or
[0071] (c) second, different, crystalline complex
Al.sub.2O.sub.3.metal oxide (again, e.g., CeAl.sub.11O.sub.18,
EuAl.sub.11O.sub.18, LaAl.sub.11O.sub.18, NdAl.sub.11O.sub.18,
PrAl.sub.11O.sub.18, or SmAl.sub.11O.sub.18) together with first
crystalline complex Al.sub.2O.sub.3.metal oxide (again, e.g.,
CeAlO.sub.3, EuAlO.sub.3, LaAlO.sub.3, NdAlO.sub.3, PrAlO.sub.3, or
SmAlO.sub.3)-second, different, crystalline complex
Al.sub.2O.sub.3.metal oxide (again, e.g., CeAl.sub.11O.sub.18,
EuAl.sub.11O.sub.18, LaAl.sub.11O.sub.18, NdAl.sub.11O.sub.18,
PrAl.sub.11O.sub.18, or SmAl.sub.11O.sub.18, respectively)
eutectic.
[0072] For abrasive particles according to the present invention
comprising yttria and nitrides and/or carbides, depending upon the
relative proportions of Al.sub.2O.sub.3, Y.sub.2O.sub.3, nitrides
and/or carbides, the resultant solidified material, and ultimately
the fused abrasive particles, may comprise:
[0073] (a) at least one of crystalline aluminum carbide, aluminum
oxycarbide, aluminum nitride, aluminum oxynitride, or a combination
thereof (e.g., aluminum oxycarbonitride)-complex
Al.sub.2O.sub.3.metal oxide (complex Al.sub.2O.sub.3.metal oxide
is, for example, Y.sub.3Al.sub.5O.sub.12) eutectic and at least one
of crystalline aluminum oxycarbide, aluminum oxynitride, or a
combination thereof (e.g., aluminum oxycarbonitride);
[0074] (b) at least one of crystalline aluminum oxycarbide,
aluminum oxynitride, or a combination thereof (e.g., aluminum
oxycarbonitride)-complex Al.sub.2O.sub.3.metal oxide (again complex
Al.sub.2O.sub.3.metal oxide is, for example,
Y.sub.3Al.sub.5O.sub.12) eutectic; and/or
[0075] (c) at least one of crystalline aluminum oxycarbide,
aluminum oxynitride, or a combination thereof (e.g., aluminum
oxycarbonitride)-complex Al.sub.2O.sub.3.metal oxide (again complex
Al.sub.2O.sub.3.metal oxide is, for example,
Y.sub.3Al.sub.5O.sub.12) eutectic and crystalline complex
Al.sub.2O.sub.3.metal oxide (again, complex Al.sub.2O.sub.3.metal
oxide is, for example, Y.sub.3Al.sub.5O.sub.12).
[0076] For abrasive particles according to the present invention
comprising rare earth oxide and nitrides and/or carbides, depending
upon the relative proportions of Al.sub.2O.sub.3, rare earth oxide,
nitrides and/or carbides, the resultant solidified material, and
ultimately the fused abrasive particles, may comprise:
[0077] (a) at least one of crystalline aluminum carbide, aluminum
oxycarbide, aluminum nitride, aluminum oxynitride, or a combination
thereof (e.g., aluminum oxycarbonitride)-complex
Al.sub.2O.sub.3.metal oxide (complex Al.sub.2O.sub.3.metal oxide
is, for example, Dy.sub.3Al.sub.5O.sub.12,
Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or Yb.sub.3Al.sub.5O.sub.12)
eutectic and at least one of crystalline aluminum oxycarbide,
aluminum oxynitride, or a combination thereof (e.g., aluminum
oxycarbonitride);
[0078] (b) at least one of crystalline aluminum oxycarbide,
aluminum oxynitride, or a combination thereof (e.g., aluminum
oxycarbonitride)-complex Al.sub.2O.sub.3.metal oxide (again complex
Al.sub.2O.sub.3.metal oxide is, for example,
Dy.sub.3Al.sub.5O.sub.12, Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or
Yb.sub.3Al.sub.5O.sub.12) eutectic; and/or
[0079] (c) at least one of crystalline aluminum oxycarbide,
aluminum oxynitride, or a combination thereof (e.g., aluminum
oxycarbonitride)-complex Al.sub.2O.sub.3.metal oxide (again complex
Al.sub.2O.sub.3.metal oxide is, for example,
Dy.sub.3Al.sub.5O.sub.12, Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or
Yb.sub.3Al.sub.5O.sub.12) eutectic and crystalline complex
Al.sub.2O.sub.3.metal oxide (again, complex Al.sub.2O.sub.3.metal
oxide is, for example, Dy.sub.3Al.sub.5O.sub.12,
Er.sub.3Al.sub.5O.sub.12, GdAlO.sub.3, or
Yb.sub.3Al.sub.5O.sub.12).
[0080] In addition to the eutectic, some fused abrasive particles
according to the present invention may further comprise at least
one of oxynitride or oxycarbide of at least one metal selected from
the group consisting of Ti, Mg, Ca, Sc, Sr, Ba, Zr, B, and
combinations thereof. In another aspect, some fused abrasive
particles according to the present invention may further comprise
at least one of boride, nitride, oxynitride, carbide, or oxycarbide
of at least one of Ti, Mg, Ca, Sc, Sr, Ba, or Zr. In yet another
aspect, some fused abrasive particles according to the present
invention may further comprise at least one of boron carbide, boron
oxycarbide, boron nitride, or boron oxynitride.
[0081] It is understood, however, the particular phases formed are
dependent upon several factors including the melt composition and
solidification conditions. Typically it is preferred that the
composition of the melt and the solidification conditions are such
that a large portion of the resulting solidified material is
occupied by eutectic (i.e., the formulation of the solidified
material corresponds to close to eutectic proportions of the
various metal oxide phases that present in the material). Although
not wanting to be bound by theory, some metastable conditions
during formation of the solidified material may lead to the
formation of alternative eutectic. For example, if under normal,
stable conditions the eutectic that forms is
Al.sub.2O.sub.3/Y.sub.3Al.sub.5O.sub.12, under some metastable
conditions Al.sub.2O.sub.3/YAlO.sub.3 eutectic may form in place
of, or in addition to Al.sub.2O.sub.3/Y.sub.3Al.sub.5O.sub.12
eutectic.
[0082] It is also with in the scope of the present invention to
substitute a portion of the aluminum and/or other metal cations in
the complex Al.sub.2O.sub.3.metal oxide with other cations. For
example, a portion of the Al cations in a complex
Al.sub.2O.sub.3.Y.sub.2O.sub.3 or Al.sub.2O.sub.3.REO may be
substituted with at least one cation of an element selected from
the group consisting of: Cr, Ti, Sc, Fe, Mg, Ca, Si, Co, and
combinations thereof. A portion of the Y cations in a complex
Al.sub.2O.sub.3.Y.sub.2O.sub.3 may be substituted with at least one
cation of an element selected from the group consisting of: Ce, Dy,
Er, Eu, Gd, Ho, La, Lu, Nd, Pr, Sm, Th, Tm, Yb, Fe, Ti, Mn, V, Cr,
Co, Ni, Cu, Mg, Ca, Sr, and combinations thereof. A portion of the
rare earth cations in a complex Al.sub.2O.sub.3.REO may be
substituted with at least one cation of an element selected from
the group consisting of: Y, Fe, Ti, Mn, V, Cr, Co, Ni, Cu, Mg, Ca,
Sr, and combinations thereof. Similarly, it is also with in the
scope of the present invention to substitute a portion of the
aluminum cations in alumina. For example, Cr, Ti, Sc, Fe, Mg, Ca,
Si, and Co can substitute for aluminum in alumina structure.
Similarly, it is also with in the scope of the present invention to
substitute a portion of the aluminum cations in aluminum
oxynitrides, oxycarbides, and/or alumina. For example, Cr, Ti, Sc,
Fe, Mg, Ca, Si, and Co can substitute for aluminum in aluminum
oxynitrides, oxycarbides, and/or alumina structure. The
substitution of cations as described above may affect the
properties (e.g. hardness, toughness, strength, thermal
conductivity, etc.) of the abrasive particles.
[0083] Further, other eutectics will be apparent to those skilled
in the art after reviewing the present disclosure. For example,
phase diagrams depicting various eutectics, including additional
eutectics for systems disclosed herein are known in the art.
[0084] Fused abrasive particles according to the present invention
containing eutectic typically material are comprised of eutectic
colonies. An individual colony contains generally homogeneous
microstructural characteristics (e.g., similar size and orientation
of crystals of constituent phases within a colony). Typically,
impurities, if present, in the fused, crystalline abrasive
particles according to the present invention, tend to segregate to
colony boundaries, and may be present alone and/or as reaction
products (e.g., as a complex Al.sub.2O.sub.3.metal oxide) as
crystalline and/or amorphous (glass) phase(s).
[0085] The constitution of eutectic colony may include: (a) two
different simple metal oxides (e.g., an Al.sub.2O.sub.3 phase and a
ZrO.sub.2 phase), (b) a simple metal oxide (e.g., an
Al.sub.2O.sub.3 phase) and a complex metal oxide (e.g., a
GdAlO.sub.3 phase), or (c) a two, different complex metal oxides
(e.g., a LaAlO.sub.3 phase and a LaAl.sub.11O.sub.18 phase).
Examples of possible eutectics for Al.sub.2O.sub.3 and
Y.sub.2O.sub.3 include Al.sub.2O.sub.3--Y.sub.3Al.sub.5O.sub.12
eutectic. Examples of possible eutectics for Al.sub.2O.sub.3 and
complex Al.sub.2O.sub.3.rare earth oxide include
Al.sub.2O.sub.3-Dy.sub.3Al.sub.5- O.sub.12,
Al.sub.2O.sub.3--Er.sub.3Al.sub.5O.sub.12,
Al.sub.2O.sub.3--GdAlO.sub.3, or
Al.sub.2O.sub.3--Yb.sub.3Al.sub.5O.sub.1- 2 eutectics. Examples of
possible eutectics for two, different complex metal oxide include a
MgAl.sub.2O.sub.4--Y.sub.3Al.sub.5O.sub.12 eutectic and
ReAlO.sub.3-ReAl.sub.11O.sub.18 eutectics, where Re.dbd.Ce, Eu, La,
Nd, Pr, or Sm.
[0086] In another aspect, phases making up the eutectic colonies
may be (a) single crystals of two different metal oxides (e.g.,
single crystals of each of Al.sub.2O.sub.3 and
Y.sub.3Al.sub.5O.sub.12, or Y.sub.3Al.sub.5O.sub.12 and at least
one of aluminum oxycarbide, aluminum oxynitride, or a combination
thereof), (b) a single crystal of one metal oxide (e.g., single
crystal Al.sub.2O.sub.3, or at least one of aluminum oxycarbide,
aluminum oxynitride, or a combination thereof) and a plurality of
crystals of a different metal oxide (e.g., polycrystalline
Y.sub.3Al.sub.5O.sub.12), or (c) two different polycrystalline
metal oxides (e.g., polycrystalline Al.sub.2O.sub.3 and
polycrystalline Y.sub.3Al.sub.5O.sub.12, or at least one of
polycrystalline aluminum oxycarbide, aluminum oxynitride, or a
combination thereof and polycrystalline
Y.sub.3Al.sub.5O.sub.12).
[0087] The colonies may be in any of a variety of shapes,
typically, ranging from essentially spherical to columnar. The
composition, phase, and/or microstructure (e.g., crystallinity
(i.e., single crystal or polycrystalline) and crystal size) of each
colony may be the same or different. The orientation of the
crystals inside the colonies may vary from one colony to another.
Phases making up a eutectic colony may be present as an
interpenetrating network(s). For example, referring to FIG. 4,
eutectic colony 150 comprises first crystalline metal oxide phase
151 and second crystalline metal oxide phase 153. The two
continuous phases form an entangled, three-dimensional network.
[0088] The number of colonies, their sizes and compositions are
affected, for example, by the melt composition and solidification
conditions. Although not wanting to be bound by theory, it is
believed that the closer the melt composition is to the exact
eutectic composition, the smaller the number of colonies that are
formed. In another aspect, however, it is believed that slow,
unidirectional solidification of the melt also tends to minimize
the number of colonies formed, while multidirectional
solidification with relatively higher cooling rates tends to
increase the number of colonies formed. The solidification rate
(i.e., cooling rate) of the melt and/or multidirectional
solidification of the melt tend to affect the type and/or number of
microstructural imperfections (e.g., pores) present in the
resulting fused abrasive particles. For example, although not
wanting to be bound by theory, relatively rapid solidification
(i.e., solidification with relatively high cooling rates) and/or
multidirectional solidification tend to lead to an increase in the
type and/or number of microstructural imperfections (e.g., pores)
present in the resulting fused abrasive particles. Relatively slow
solidification, however, tends to lead to an increase in the size
of the colonies, and/or crystals present in the solidified
material; although it may be possible through slow and controlled
cooling, for example, to eliminate formation of colonies. Hence, in
selecting the cooling rate and/or degree of multidirectional
solidification, there may be a need to increase or decrease the
cooling rate to obtain the optimal balance of desirable and
undesirable microstructural characteristics associated with the
various cooling rates.
[0089] Further, for a given composition, the size of the colonies
and phases present within the colonies tends to decrease as the
cooling rate of the melt increases. Typically, the eutectic
colonies in abrasive particles according to the present invention
are, on average, less than 100 micrometers, preferably, less than
50 micrometers, wherein such size for a given colony is the average
of the two largest dimensions measured from a polished
cross-section of the colony, as viewed with a scanning electron
microscope (SEM). Typically, the smallest dimension of the
crystalline phases making up the eutectic in a colony, as measured
from a polished cross-section of the colony viewed with an SEM, is
up to 10 micrometers; preferably, up to 5 micrometers; more
preferably, up to 1 micrometer, or even up to 0.5 micrometer.
[0090] Some abrasive particles according to the present invention
also include primary crystals of at least one of the metal oxide
phases making up the eutectic constituent of the abrasive particle.
For example, if the eutectic portion is made up of a LaAlO.sub.3
phase and a LaAl.sub.11O.sub.18 phase, the microstructure may also
include primary crystals of LaAlO.sub.3, which is believed to occur
when the composition of the melt from which the abrasive particles
are formed is rich in La.sub.2O.sub.3 (i.e., the melt contains, on
a theoretical oxide basis, an excess of La.sub.2O.sub.3 relative to
the eutectic); or if the eutectic is made up of a
Yb.sub.3Al.sub.5O.sub.12 phase, and Al.sub.2O.sub.3, the
microstructure may also include primary crystals of
Al.sub.2O.sub.3, which is believed to occur when the composition of
the melt from which the abrasive particles are formed is rich in
Al.sub.2O.sub.3 (i.e., the melt contains, on a theoretical oxide
basis, an excess of Al.sub.2O.sub.3 relative to the eutectic).
[0091] The formation of the primary crystals is believed to result
from a deviation from the particular eutectic proportions. The
greater the deviation, the larger the overall fraction of primary
crystals. The primary crystals may be found in a variety of shapes,
typically ranging from rod-like structures to dendritic-like
structures. Although not wanting to be bound by theory, it is
believed that the presence and/or formation of a primary crystal(s)
adjacent to a colony may affect the resulting microstructure of the
colony. In some cases it may be advantageous (e.g., for increased
abrading performance) to have primary crystals (e.g., primary
Al.sub.2O.sub.3 crystals) present in the abrasive particles. It is
also believed, however, that the abrading performance of an
abrasive particle tends to decrease as the size of the primary
crystals increase.
[0092] Further, although not wanting to be bound by theory, it is
believed that small additions (e.g., less than 5 percent by weight)
of metal oxides other than those making up the eutectic may affect
colony boundaries, and in turn affect properties (e.g., hardness
and toughness) of the abrasive particle.
[0093] Sources of (on a theoretical oxide basis) Al.sub.2O.sub.3
for making abrasive particles according to the present invention
include those known in the art for making conventional fused
alumina and alumina-zirconia abrasive particles. Commercially
available Al.sub.2O.sub.3 sources include bauxite (including both
natural occurring bauxite and synthetically produced bauxite),
calcined bauxite, hydrated aluminas (e.g., boehmite, and gibbsite),
Bayer process alumina, aluminum ore, gamma alumina, alpha alumina,
aluminum salts, aluminum nitrates, and combinations thereof. The
Al.sub.2O.sub.3 source may contain, or only provide,
Al.sub.2O.sub.3. Alternatively, the Al.sub.2O.sub.3 source may
contain, or provide Al.sub.2O.sub.3, as well as one or more metal
oxides other than Al.sub.2O.sub.3 (including materials of or
containing complex Al.sub.2O.sub.3.metal oxides (e.g.,
Dy.sub.3Al.sub.5O.sub.12, Y.sub.3Al.sub.5O.sub.12,
CeAl.sub.11O.sub.18 , etc.)).
[0094] Preferred metal oxides in addition to the Al.sub.2O.sub.3
(i.e., preferred "metal oxides other than Al.sub.2O.sub.3") include
Y.sub.2O.sub.3 and rare earth oxide.
[0095] Commercially available sources of (on a theoretical oxide
basis) Y.sub.2O.sub.3 for making abrasive particles according to
the present invention include yttrium oxide powders, yttrium,
yttrium-containing ores, and yttrium salts (e.g., yttrium
carbonates, nitrates, chlorides, hydroxides, and combinations
thereof). The Y.sub.2O.sub.3 source may contain, or only provide,
Y.sub.2O.sub.3. Alternatively, the Y.sub.2O.sub.3 source may
contain, or provide Y.sub.2O.sub.3, as well as one or more metal
oxides other than Y.sub.2O.sub.3 (including materials of or
containing complex Y.sub.2O.sub.3.metal oxides (e.g.,
Y.sub.3Al.sub.5O.sub.12)).
[0096] Commercially available sources of rare earth oxides for
making abrasive particles according to the present invention
include rare earth oxide powders, rare earth metals, rare
earth-containing ores (e.g., bastnasite and monazite), rare earth
salts, rare earth nitrates, and rare earth carbonates. The rare
earth oxide(s) source may contain, or only provide, rare earth
oxide(s). Alternatively, the rare earth oxide(s) source may
contain, or provide rare earth oxide(s), as well as one or more
metal oxides other than rare earth oxide(s) (including materials of
or containing complex rare earth oxide .cndot. other metal oxides
(e.g., Dy.sub.3Al.sub.5O.sub.12, CeAl.sub.11O.sub.18, etc.)).
[0097] Commercially available sources of metal nitrides and metal
carbides for making abrasive particles according to the present
invention include powders and ores comprised of at least one of
metal (e.g., aluminum) carbide or nitride and/or at least one other
metal other than Al. Other materials containing carbon (e.g.,
graphite powder) and/or nitrogen (e.g., nitrogen gas) may also be
used as a raw materials for making abrasive particles according to
the present invention.
[0098] The addition of certain metal oxides may alter the
crystalline structure or microstructure of the resulting fused
abrasive particles. For example, although not wishing to be bound
by any theory, it is theorized that certain metal oxides or metal
oxide containing compounds (even when used in relatively small
amounts, for example, even 0.01 to 5 percent by weight, based on
the total metal oxide content of the fused abrasive particle) may
be present at the boundaries between the eutectic colonies. The
presence of these metal oxides, which may be in the form of
reaction products together or with the Al.sub.2O.sub.3 may affect
the fracture characteristics and/or microstructure of the fused
abrasive particles, and/or may affect the grinding characteristics
of the abrasive particles. Certain metal oxides may also act as a
processing aid, for example, to increase the density of the fused
abrasive particles, by decreasing the size and/or number of pores
in the fused abrasive particles. Certain metal oxides may also act
as a processing aid, for example, to increase or decrease the
effective melting temperature of the melt. Thus certain metal
oxides may be added for processing reasons.
[0099] Fused abrasive particles according to the present invention
typically comprise less than 50 percent by weight (more typically,
less than 20 percent by weight; in some cases in the range from
0.01 to5 percent by weight, in other cases from 0.1 to 1 percent by
weight) of metals oxides (on a theoretical oxide basis) other than
the eutectic forming metal oxides, based on the total metal oxide
content of the respective abrasive particle. Sources of the metal
oxides other than Al.sub.2O.sub.3, Y.sub.2O.sub.3, and rare earth
oxides are also readily commercially available.
[0100] Examples of other than Al.sub.2O.sub.3, Y.sub.2O.sub.3, rare
earth oxides metal oxides include, on a theoretical oxide basis,
BaO, CaO, Cr.sub.2O.sub.3, CoO, Fe.sub.2O.sub.3, HfO.sub.2,
Li.sub.2O, MgO, MnO, NiO, SiO.sub.2, TiO.sub.2, Na.sub.2O,
Sc.sub.2O.sub.3, SrO, V.sub.2O.sub.3, ZnO, ZrO.sub.2, and
combinations thereof.
[0101] Materials for making abrasive particles according to the
present invention also include fused abrasive particles (e.g.,
fused alumina abrasive particles) or other fused material (e.g.,
fused alumina material) having the same composition or different
composition(s), which together with remaining metal oxide, carbide,
and nitride sources, as the case may be, provide the desired
composition of the fused abrasive particles.
[0102] A reducing agent, such as a carbon source may be added to
reduce impurities during the melting process. Examples of carbon
sources include: coal, graphite, petroleum coke, or the like.
Typically, the amount of carbon included in the charge to the
furnace is up 5% by weight of the charge; more typically, up to 3%
by weight, and more typically, up to 2% by weight. Iron may also be
added to the furnace charge to aid in the removal of impurities.
The iron can combine with the impurities to make a material that
can be removed magnetically, for example, from the melt or crushed
solidified material.
[0103] It is also within the scope of the present invention to
include metal borides, carbides, nitrides, and combinations thereof
in the fused, crystalline abrasive particles according to the
present invention. Such materials may even be present within (e.g.;
as inclusions) the eutectic material. Examples of metal borides,
carbides, and nitrides may include titanium diboride, aluminum
carbide, aluminum nitride, titanium carbide, titanium nitride,
silicon carbide, boron carbide, and boron nitride. Such materials
are known in the art, and are commercially available.
[0104] The particular selection of metal oxide sources and other
additives for making fused abrasive particles according to the
present invention typically takes into account, for example, the
desired composition and microstructure of the resulting abrasive
particles, the desired physical properties (e.g., hardness or
toughness) of the resulting abrasive particles, avoiding or
minimizing the presence of undesirable impurities, the desired
grinding characteristics of the resulting abrasive particles,
and/or the particular process (including equipment and any
purification of the raw materials before and/or during fusion
and/or solidification) being used to prepare the abrasive
particles.
[0105] The metal oxide sources and other additives can be in any
form suitable to the process and equipment being used to make the
abrasive particles. The raw materials can be fused using techniques
and equipment known in the art for making conventional fused
alumina and alumina-zirconia abrasive particles (see, e.g., U.S.
Pat. Nos. 3,781,172 (Pett et al.), 3,891,408 (Rowse et al.),
4,035,162 (Brothers et al.), 4,070,796 (Scott), 4,073,096 (Ueltz et
al.), 4,126,429 (Watson), 4,457,767 (Poon et al.), 5,143,522
(Gibson et al.), and Re. 31,128 (Walker et al.), the disclosures of
which are incorporated herein by reference).
[0106] Examples of furnaces for melting the metal oxide sources and
other additives include arc furnaces, pig furnaces, arc tapping
furnaces, electric furnaces, electric arc furnaces, and gas fired
furnaces. Suitable electric furnaces include those in which the
electrodes are arranged to create a "kissing arc", wherein the
lower tip of the electrodes are not in contact within the molten
mass, as well as those in which the electrodes are submerged in the
molten mass to provide resistance heating via current passing
through the melt.
[0107] The furnace may have a lining (sometimes referred to as a
"shell" or "skeleton") that covers the inside of the furnace walls.
The lining may be made from a material dissimilar to the fused
abrasive particle composition. Typically, however it is preferred
that the furnace lining is made from a composition or material
similar, sometimes nearly identical or identical to the composition
of the fused abrasive particle. Thus during processing, if the
outer (exposed) surface of the lining melts, the potential
contamination of the melt is reduced or minimized.
[0108] For some metal oxide sources and other additives, it may
also be desirable to preheat feed prior to charging it into the
furnace, or otherwise combining it with other metal oxide sources
and other additives. For example, if carbonate, nitrate or other
salts are used as the metal oxide source, it may be desirable to
calcine (e.g., by heating them in air at about 400-1000.degree. C.)
such materials prior to adding them with the other metal oxide
source materials.
[0109] Generally, the metal oxide sources and other additives, if
present, are heated to a molten state, and mixed until the melt is
homogenous. Typically, the melt is heated to and held at a
temperature at least 50.degree. C. (preferably, at least
100.degree. C.) above the melting point of the melt. If the
temperature of the melt is too low, the viscosity of the melt may
be undesirably too high, making it more difficult to homogenize the
various metal oxide sources and other additives making up the melt,
or to pour or otherwise transfer the melt from the furnace. If the
temperature of the melt is too high temperature, and/or the melt
heated for too long, energy will be wasted, and there may be
undesirable volatilization of components of the melt as well.
[0110] In some cases, it may be desirable, to mix, or otherwise
blend the metal oxide sources and other additives (e.g., volatile
components (e.g., water or organic solvent) which may assist in
forming a homogenous mixture or blend), if present, together prior
to forming the melt. For example, particulate metal oxide sources
can be milled (e.g., ball milled) to both mix the materials
together, as well as reduce the size of the particulate material.
Other techniques for mixing or blending the metal oxide sources and
other additives, if present, together prior to forming the melt
include high shear mixers, paddle mixers, V-blenders, tumblers, and
the like. Milling times may range from several minutes to several
hours, or even days. Optionally, fugitive materials such as water
and organic solvents may be removed from the mixture or blend of
metal oxide sources and other additives, for example, by heating,
prior to forming the melt. For ease of handling, the metal oxide
sources and other additives may also be agglomerated prior to
charging them to the furnace.
[0111] The atmosphere over the melt may be at atmospheric pressure,
a pressure above atmospheric pressure, or a pressure below
atmospheric pressure, although a pressure below atmospheric
pressure may be preferred in order to reduce the number of pores in
the resulting solidified material. The atmosphere over the melt may
also be controlled to provide an oxidizing, reducing or inert
atmosphere which may affect the melt chemistry.
[0112] Reducing conditions during melting may aid in purifying the
melt. In addition to, or alternatively to, adding a reducing agent
to the melt, suitable reducing conditions may be obtained using
carbon electrodes with an electric arc melting furnace. Under
suitable reducing conditions, some impurities (e.g., silica, iron
oxide, and titania) will convert to their respective molten
metallic form, leading to a higher specific gravity for the melt.
Such free metal(s) impurities would then tend to sink to the bottom
of the furnace.
[0113] In another aspect, it may be desired to oxidize free metal
present in the melt before the melt is cooled (e.g., before pouring
the melt from the furnace). For example, an oxygen lance(s) may be
inserted into the melt just prior to pouring the melt from the
furnace (see, e.g., U.S. Pat. No. 960,712, the disclosure of which
is incorporated herein by reference).
[0114] The melt can be cooled using any of a variety of techniques
known in the art. Typically the furnace containing the melt is
capable of being tilted such that the melt can be poured over or
into a heat sink. Generally, the resulting solidified material is
larger in size than the desired abrasive particles. Examples of
heat sinks include metallic balls (e.g., cast iron or carbon steel
balls), metallic rods, metallic plates, metallic rolls, and the
like. In some instances, these heat sink materials may be
internally cooled (e.g., water-cooled or a suitable refrigerant) to
achieve fast cooling rates. The heat sink material may also be
pieces of pre-fused abrasive particles (having the same or a
different composition being solidified) or other refractory
material.
[0115] Further with regard to heat sinks, the melt can be cooled by
pouring the melt over and in between a plurality of metallic balls.
The balls typically range in diameter from about 1 to 50 cm, more
typically 5 to 25 cm. The melt may also be cooled using book molds.
Suitable book molds consist of a plurality of thin plates (e.g.,
metallic or graphite plates) that are spaced relatively close
together. The plates are usually spaced less than 10 cm apart,
typically less than 5 cm, and preferably less than 1 cm apart. The
melt may also be poured into graphite or cast iron molds to form
slabs. It is generally preferred that such "slabs" be relatively
thin so as to achieve faster cooling rates.
[0116] The cooling rate is believed to affect the microstructure
and physical properties of the solidified material, and thus the
fused abrasive particles. Preferably, the melt is rapidly cooled as
the size of the crystalline phases of the solidified material
generally decreases as the cooling rate increase. Preferred cooling
rates are at least 500.degree. C./min.; more preferably, at least
1000.degree. C./min; and even more preferably, at least
1500.degree. C./min. The cooling rate may depend upon several
factors including the chemistry of the melt, the melting point of
the melt, the type of heat sink, and the heat sink material.
[0117] Rapid cooling may also be conducted under controlled
atmospheres, such as a reducing, neutral or oxidizing environment
to maintain and/or influence the desired crystalline phases,
oxidation states, etc. during cooling.
[0118] Additional details on cooling a melt can be found, for
example, in U.S. Pat. Nos. Re 31,128 (Walker et al.), 3,781,172
(Pett et al.), 4,070,796 (Scott et al.), 4,194,887 (Ueltz et al.),
4,415,510 (Richmond), 4,439,845 (Richmond), and 5,143,522 (Gibson
et al.), the disclosures of which are incorporated herein by
reference.
[0119] The resulting (solidified) fused material(s) is typically
larger in size than that desired for the abrasive particle(s). The
fused material can be, and typically is, converted into smaller
pieces using crushing and/or comminuting techniques known in the
art, including roll crushing, canary milling, jaw crushing, hammer
milling, ball milling, jet milling, impact crushing, and the like.
In some instances, it is desired to have two or multiple crushing
steps. For example after the molten material is solidified, it may
be in the form of a relatively large mass structure (e.g., a
diameter greater than 5 cm. The first crushing step may involve
crushing these relatively large masses or "chunks" to form smaller
pieces. This crushing of these chunks may be accomplished with a
hammer mill, impact crusher or jaw crusher. These smaller pieces
may then be subsequently crushed to produce the desired particle
size distribution. In order to produce the desired particle size
distribution (sometimes referred to as grit size or grade), it may
be necessary to perform multiple crushing steps. In general the
crushing conditions are optimized to achieve the desired particle
shape(s) and particle size distribution.
[0120] The shape of fused abrasive particles according to the
present invention depends, for example, on the composition and/or
microstructure of the abrasive particles, the geometry in which it
was cooled, and the manner in which the solidified material is
crushed (i.e., the crushing technique used). In general, where a
"blocky" shape is preferred, more energy may be employed to achieve
this shape. Conversely, where a "sharp" shape is preferred, less
energy may be employed to achieve this shape. The crushing
technique may also be changed to achieve different desired shapes.
Alternatively, abrasive particles may be directly formed into
desired shapes by pouring or forming the melt into a mold.
[0121] The shape of the abrasive particles may be measured by
various techniques known in the art, including bulk density and
aspect ratio. The larger the abrasive particle size, the higher the
bulk density due to the increased mass associated with larger
particle sizes. Thus, when comparing bulk densities, the comparison
should be made on abrasive particles having essentially the same
particle size. In general, the larger the bulk density number, the
"blockier" the abrasive particle is considered to be. Conversely
the smaller the bulk density number, the "sharper" the abrasive
particle is considered to be. Another way to measure sharpness is
through an aspect ratio. The aspect ratio of a grade 36 for
example, may range from about 1:1 to about 3:1, typically about
1.2:1 to about 2:1.
[0122] The bulk density of the abrasive particles can be measured
in accordance with ANSI Standard B74.4-1992 (1992), the disclosure
of which is incorporated herein by reference. In general, the bulk
density is measured by pouring the abrasive particles sample
through a funnel so that the abrasive particles traverses through
the funnel in a free flowing manner. Immediately underneath the
funnel is a collection device (typically a graduated cylinder). A
predetermined volume of abrasive particles arc collected and then
weighed. The bulk density is calculated in terms of
weight/volume.
[0123] Abrasive particles according to the present invention can be
screened and graded using techniques well known in the art,
including the use of industry recognized grading standards such as
ANSI (American National Standard Institute), FEPA (Federation
Europeenne des Fabricants de Products Abrasifs), and JIS (Japanese
Industrial Standard). Abrasive particles according to the present
invention may be used in a wide range of particle sizes, typically
ranging in size from about 0.1 to about 5000 micrometers, more
typically from about 1 to about 2000 micrometers; preferably from
about 5 to about 1500 micrometers, more preferably from about 100
to about 1500 micrometers.
[0124] In a given particle size distribution, there will be a range
of particle sizes, from coarse particles fine particles. In the
abrasive art this range is sometimes referred to as a "coarse",
"control" and "fine" fractions. Abrasive particles graded according
to industry accepted grading standards specify the particle size
distribution for each nominal grade within numerical limits. Such
industry accepted grading standards include those known as the
American National Standards Institute, Inc. (ANSI) standards,
Federation of European Producers of Abrasive Products (FEPA)
standards, and Japanese Industrial Standard (JIS) standards. ANSI
grade designations (i.e., specified nominal grades) include: ANSI
4, ANSI 6, ANSI 8, ANSI 16, ANSI 24, ANSI 36, ANSI 40, ANSI 50,
ANSI 60, ANSI 80, ANSI 100, ANSI 120, ANSI 150, ANSI 180, ANSI 220,
ANSI 240, ANSI 280, ANSI 320, ANSI 360, ANSI 400, and ANSI 600.
Preferred ANSI grades comprising abrasive particles according to
the present invention are ANSI 8-220. FEPA grade designations
include P8, P12, P16, P24, P36, P40, P50, P60, P80, P100, P120,
P150, P180, P220, P320, P400, P500, P600, P800, P1000, and P1200.
Preferred FEPA grades comprising abrasive particles according to
the present invention are P12-P220. JIS grade designations include
JIS8, JIS12, JIS16, JIS24, JIS36, JIS46, JIS54, JIS60, JIS80,
JIS100, JIS150, JIS180, JIS220, JIS 240, JIS280, JIS320, JIS360,
JIS400, JIS400, JIS600, JIS800, JIS1000, JIS1500, JIS2500, JIS4000,
JIS6000, JIS8000, and JIS10,000. Preferred JIS grades comprising
abrasive particles according to the present invention are
JIS8-220.
[0125] After crushing and screening, there will typically be a
multitude of different abrasive particle size distributions or
grades. These multitudes of grades may not match a manufacturer's
or supplier's needs at that particular time. To minimize inventory,
it is possible to recycle the off demand grades back into the
molten mass. This recycling may occur after the crushing step,
where the particles are in large chunks or smaller pieces
(sometimes referred to as "fines") that have not been screened to a
particular distribution. A charge to the furnace for making fused
abrasive particles according to the present invention may consist
of anywhere from 0 to 100% by weight recycled fused abrasive
particles, typically between 0 to 50% by weight.
[0126] Typically, the true density, sometimes referred to as
specific gravity, of fused abrasive particles according to the
present invention is typically at least 80% of theoretical density,
although abrasive particles with a lower true density may also be
useful in abrasive applications. Preferably, the true density of
fused abrasive particles according to the present invention is at
least 85% of theoretical density, more preferably at least 90% of
theoretical density, and even more preferably at least 95% of
theoretical density.
[0127] Typically, fused abrasive particles according to the present
invention may have an average toughness (i.e., resistance to
fracture) of at least 2.0 MPa m.sup.1/2; preferably at least 2.5
MPa m.sup.1/2, more preferably at least 3.0 MPa m.sup.1/2, and even
more preferably, at least 3.3 MPa m.sup.1/2, at least 3.5 MPa
m.sup.1/2, or even at least 3.8 MPa m.sup.1/2.
[0128] It is also within the scope of the present invention to
provide a surface coating on the fused abrasive particles. Surface
coatings are known, for example, to improve the adhesion between
the abrasive particles and the binder material in the abrasive
article. Such surface coatings are described, for example, in U.S.
Pat. Nos. 1,910,444 (Nicholson), 3,041,156 (Rowse et al.),
4,997,461 (Markhoff-Matheny et al.), 5,009,675 (Kunz et al.),
5,042,991 (Kunz et al.), and 5,085,671 (Martin et al.), the
disclosures of which are incorporated herein by reference. Further,
in some instances, the addition of the coating improves the
abrading characteristics of the abrasive particles. Alternatively
the surface coating may improve adhesion between the abrasive
particle of the invention and the binder.
[0129] Likewise after the abrasive particles are produced, it may
be further heat-treated to improve its physical properties and/or
grinding performance. This heat-treating process may occur in an
oxidizing atmosphere. Typically this heat-treating process occurs
at a temperature between about 1100.degree. C. to 1600.degree. C.,
usually between 1200.degree. C. to 1400.degree. C. The time may
range from about 1 minute to days, usually between about 5 minutes
to 1 hour.
[0130] Other suitable preparation techniques for making fused
abrasive particles according to the present invention may be
apparent to those skilled in the art after reviewing the disclosure
herein, as well as, for example, applications having U.S. Ser. Nos.
09,495,978, 09/496,422, 09/496,638, and 09/496,713, each filed on
Feb. 2, 2000, and, ______ (Attorney Docket Nos. 55333USA2B,
55763USA3A, 55353USA1B, 55765USA9A, 55764USA1A, 55605USA7A,
55606USA5A, 55607USA3A, 55608USA1A, and 55356USA4B, each filed on
the same date as the instant application, the disclosure of which
are all incorporated herein by reference
[0131] Preferred abrasive particles according to the present
invention are thermally stable at elevated temperatures, as
compared to conventional fused alumina-zirconia materials
(including alumina-zirconia abrasive particles available from
Norton Company, Worcester, Mass. under the trade designation
"NORZON"). When alumina-zirconia eutectic abrasive particles
available from Norton Company, Worcester, Mass. under the trade
designation "NORZON, are heated in air, for example, to at least
about 350.degree. C., typically at least a portion of the zirconia
undergoes a tetragonal and/or cubic to monoclinic phase
transformation. This phase transformation is usually detrimental to
the structural integrity of the alumina-zirconia material because
it involves volume changes to the zirconia crystalline phases.
Further, such phase transformations have been observed to occur
preferentially at the boundaries of eutectic colonies, which
thereby tend to weaken the boundaries, and which in turn tend to
lead to significant degradation of mechanical properties (i.e.,
hardness, strength, etc.) of the material. In addition, various
impurities, which are typically segregated during solidification of
the melt into the eutectic colonies boundaries may also undergo
volumetric structural changes (e.g., due to oxidation), leading to
further degradation of mechanical properties (i.e., hardness,
strength, etc.) of the material.
[0132] By contrast, preferred abrasive particles according to the
present invention typically do not exhibit phase transformations of
the eutectic phases when heated up to 1000.degree. C. (in some
cases even up to 1400.degree. C.) in air, and thus are thermally
stable. Although not wishing to be bound by any theory, it is
believed that this thermal stability allows such abrasive particle
to be incorporated into vitrified bonded abrasives.
[0133] The thermal stability of certain preferred abrasive
particles according to the present invention may be measured or
illustrated using a variety of different techniques, including:
Differential Thermal Analysis (DTA), Thermogravimetric Analysis
(TGA), X-ray diffraction, hardness measurements, microstructure
analysis, color change, and interaction with glass bonds. The
thermal stability of the abrasive particles may be dependent, for
example, upon the composition, particle chemistry, and processing
conditions.
[0134] For example, as disclosed above, the fused abrasive
particles according to the present invention have a first average
microhardness of at least 11 GPa (preferably, at least 12, 13, or
14 GPa, more preferably, at least 15 GPa, and even more preferably,
at least 16 GPa, at least 17 GPa, or even at least 18 GPa), wherein
the abrasive particles have a second average microhardness after
being heated in air at 1000.degree. C. in air for 4 hours, and
wherein the second average microhardness is at least 85%
(preferably, at least 90%; more preferably, at least 95%; and even
more preferably, about 100%) of the first average microhardness
(see Example 3 (below) for a more complete description of the
test
[0135] The thermal stability of certain preferred abrasive
particles according to the present invention may also be observed
using Scanning Electron Microscopy (SEM), wherein the average
microstructure (e.g., porosity, crystal structure, colony size and
crystal size (eutectic crystals, and primary crystals, if present)
and integrity of the abrasive particles is examined before and
after being heated at 1000.degree. C. in air for 4 hours. The
microstructure of certain preferred abrasive particles according to
the present invention are essentially the same before and after
being heated at 1000.degree. C. in air for 4hours.
[0136] Further, the thermal stability of certain preferred abrasive
particles according to the present invention may also be
illustrated by comparing the color of the abrasive particles before
and after they are heated at 1000.degree. C. in air for 4 hours.
The microstructure of preferred abrasive particles according to the
present invention is essentially the same before and after being
heated at 1000.degree. C. in air for 4 hours.
[0137] The thermal stability of certain preferred abrasive
particles according to the present invention may also be
illustrated by comparing powder XRD result of the abrasive
particles before and after they are heated at 1000.degree. C. in
air for 4 hours. As discussed above, when alumina-zirconia eutectic
material is heated in air, typically at least a portion of the
zirconia undergoes a tetragonal and/or cubic to monoclinic phase
transformation. The effect of this phase transformation is
typically significant enough to be observed via powder XRD. By
contrast, the eutectic phases of certain preferred abrasive
particles according to the present invention do not exhibit such
phase transformations when heated to 1000.degree. C. in air, hence
no transformation of the eutectic phases will be observed in the
XRD results.
[0138] Fused abrasive particles according to the present invention
can be used in conventional abrasive products, such as coated
abrasive products, bonded abrasive products (including vitrified,
resinoid, and metal bonded grinding wheels, cutoff wheels, mounted
points, and honing stones), nonwoven abrasive products, and
abrasive brushes. Typically, abrasive products (i.e., abrasive
articles) include binder and abrasive particles, at least a portion
of which is fused abrasive particles according to the present
invention, secured within the abrasive product by the binder.
Methods of making such abrasive products and using abrasive
products are well known to those skilled in the art. Furthermore,
fused abrasive particles according to the present invention can be
used in abrasive applications that utilize abrasive particles, such
as slurries of abrading compounds (e.g., polishing compounds),
milling media, shot blast media, vibratory mill media, and the
like.
[0139] Coated abrasive products generally include a backing,
abrasive particles, and at least one binder to hold the abrasive
particles onto the backing. The backing can be any suitable
material, including cloth, polymeric film, fibre, nonwoven webs,
paper, combinations thereof, and treated versions thereof. The
binder can be any suitable binder, including an inorganic or
organic binder (including thermally curable resins and radiation
curable resins). The abrasive particles can be present in one layer
or in two layers of the coated abrasive product.
[0140] An example of a coated abrasive product is depicted in FIG.
1. Referring to this figure, coated abrasive product 1 has a
backing (substrate) 2 and abrasive layer 3. Abrasive layer 3
includes fused abrasive particles according to the present
invention 4 secured to a major surface of backing 2 by make coat 5
and size coat 6. In some instances, a supersize coat (not shown) is
used.
[0141] Bonded abrasive products typically include a shaped mass of
abrasive particles held together by an organic, metallic, or
vitrified binder. Such shaped mass can be, for example, in the form
of a wheel, such as a grinding wheel or cutoff wheel. The diameter
of grinding wheels typically is about 1 cm to over 1 meter; the
diameter of cut off wheels about 1 cm to over 80 cm (more typically
3 cm to about 50 cm). The cut off wheel thickness is typically
about 0.5 mm to about 5 cm, more typically about 0.5 mm to about 2
cm. The shaped mass can also be in the form, for example, of a
honing stone, segment, mounted point, disc (e.g. double disc
grinder) or other conventional bonded abrasive shape. Bonded
abrasive products typically comprise about 3-50% by volume bond
material, about 30-90% by volume abrasive particles (or abrasive
particle blends), up to 50% by volume additives (including grinding
aids), and up to 70% by volume pores, based on the total volume of
the bonded abrasive product.
[0142] A preferred form is a grinding wheel. Referring to FIG. 2,
grinding wheel 10 is depicted, which includes fused abrasive
particles according to the present invention 11, molded in a wheel
and mounted on hub 12.
[0143] Nonwoven abrasive products typically include an open porous
lofty polymer filament structure having fused abrasive particles
according to the present invention distributed throughout the
structure and adherently bonded therein by an organic binder.
Examples of filaments include polyester fibers, polyamide fibers,
and polyaramid fibers. In FIG. 3, a schematic depiction, enlarged
about 100.times., of a typical nonwoven abrasive product is
provided. Such a nonwoven abrasive product comprises fibrous mat 50
as a substrate, onto which fused abrasive particles according to
the present invention 52 are adhered by binder 54.
[0144] Useful abrasive brushes include those having a plurality of
bristles unitary with a backing (see, e.g., U.S. Pat. Nos.
5,427,595 (Pihl et al.), 5,443,906 (Pihl et al.), 5,679,067
(Johnson et al.), and 5,903,951 (Ionta et al.), the disclosure of
which is incorporated herein by reference). Preferably, such
brushes are made by injection molding a mixture of polymer and
abrasive particles.
[0145] Suitable organic binders for making abrasive products
include thermosetting organic polymers. Examples of suitable
thermosetting organic polymers include phenolic resins,
urea-formaldehyde resins, melamine-formaldehyde resins, urethane
resins, acrylate resins, polyester resins, aminoplast resins having
pendant .alpha.,.beta.-unsaturated carbonyl groups, epoxy resins,
acrylated urethane, acrylated epoxies, and combinations thereof.
The binder and/or abrasive product may also include additives such
as fibers, lubricants, wetting agents, thixotropic materials,
surfactants, pigments, dyes, antistatic agents (e.g., carbon black,
vanadium oxide, graphite, etc.), coupling agents (e.g., silanes,
titanates, zircoaluminates, etc.), plasticizers, suspending agents,
and the like. The amounts of these optional additives are selected
to provide the desired properties. The coupling agents can improve
adhesion to the abrasive particles and/or filler. The binder
chemistry may thermally cured, radiation cured or combinations
thereof. Additional details on binder chemistry may be found in
U.S. Pat. Nos. 4,588,419 (Caul et al.), 4,751,137 (Tumey et al.),
and 5,436,063 (Follett et al.), the disclosures of which are
incorporated herein by reference.
[0146] More specifically with regard to vitrified bonded abrasives,
vitreous bonding materials, which exhibit an amorphous structure
and are typically hard, are well known in the art. In some cases,
the vitreous bonding material includes crystalline phases. Bonded,
vitrified abrasive products according to the present invention may
be in the shape of a wheel (including cut off wheels), honing
stone, mounted pointed or other conventional bonded abrasive shape.
A preferred vitrified bonded abrasive product according to the
present invention is a grinding wheel.
[0147] Examples of metal oxides that are used to form vitreous
bonding materials include: silica, silicates, alumina, soda,
calcia, potassia, titania, iron oxide, zinc oxide, lithium oxide,
magnesia, boria, aluminum silicate, borosilicate glass, lithium
aluminum silicate, combinations thereof, and the like. Typically,
vitreous bonding materials can be formed from composition
comprising from 10 to 100% glass frit, although more typically the
composition comprises 20% to 80% glass frit, or 30% to 70% glass
frit. The remaining portion of the vitreous bonding material can be
a non-frit material. Alternatively, the vitreous bond may be
derived from a non-frit containing composition. Vitreous bonding
materials are typically matured at a temperature(s) in the range
from about 700.degree. C. to about 1500.degree. C., usually in the
range from about 800.degree. C. to about 1300.degree. C., sometimes
in the range from about 900.degree. C. to about 1200.degree. C., or
even in the range from about 950.degree. C. to about 1100.degree.
C. The actual temperature at which the bond is matured depends, for
example, on the particular bond chemistry.
[0148] Preferred vitrified bonding materials may include those
comprising silica, alumina (preferably, at least 10 percent by
weight alumina), and boria (preferably, at least 10 percent by
weight boria). In most cases the vitrified bonding material further
comprise alkali metal oxide(s) (e.g., Na.sub.2O and K.sub.2O) (in
some cases at least 10 percent by weight alkali metal
oxide(s)).
[0149] Binder materials may also contain filler materials or
grinding aids, typically in the form of a particulate material.
Typically, the particulate materials are inorganic materials.
Examples of useful fillers for this invention include: metal
carbonates (e.g., calcium carbonate (e.g., chalk, calcite, marl,
travertine, marble and limestone), calcium magnesium carbonate,
sodium carbonate, magnesium carbonate), silica (e.g., quartz, glass
beads, glass bubbles and glass fibers) silicates (e.g., talc,
clays, (montmorillonite) feldspar, mica, calcium silicate, calcium
metasilicate, sodium aluminosilicate, sodium silicate) metal
sulfates (e.g., calcium sulfate, barium sulfate, sodium sulfate,
aluminum sodium sulfate, aluminum sulfate), gypsum, vermiculite,
wood flour, aluminum trihydrate, carbon black, metal oxides (e.g.,
calcium oxide (lime), aluminum oxide, titanium dioxide), and metal
sulfites (e.g., calcium sulfite).
[0150] In general, the addition of a grinding aid increases the
useful life of the abrasive product. A grinding aid is a material
that has a significant effect on the chemical and physical
processes of abrading, which results in improved performance.
Although not wanting to be bound by theory, it is believed that a
grinding aid(s) will (a) decrease the friction between the abrasive
particles and the workpiece being abraded, (b) prevent the abrasive
particles from "capping" (i.e., prevent metal particles from
becoming welded to the tops of the abrasive particles), or at least
reduce the tendency of abrasive particles to cap, (c) decrease the
interface temperature between the abrasive particles and the
workpiece, or (d) decreases the grinding forces.
[0151] Grinding aids encompass a wide variety of different
materials and can be inorganic or organic based. Examples of
chemical groups of grinding aids include waxes, organic halide
compounds, halide salts and metals and their alloys. The organic
halide compounds will typically break down during abrading and
release a halogen acid or a gaseous halide compound. Examples of
such materials include chlorinated waxes like
tetrachloronaphtalene, pentachloronaphthalene, and polyvinyl
chloride. Examples of halide salts include sodium chloride,
potassium cryolite, sodium cryolite, ammonium cryolite, potassium
tetrafluoroboate, sodium tetrafluoroborate, silicon fluorides,
potassium chloride, and magnesium chloride. Examples of metals
include, tin, lead, bismuth, cobalt, antimony, cadmium, and iron
titanium. Other miscellaneous grinding aids include sulfur, organic
sulfur compounds, graphite, and metallic sulfides. It is also
within the scope of the present invention to use a combination of
different grinding aids, and in some instances this may produce a
synergistic effect. The preferred grinding aid is cryolite; the
most preferred grinding aid is potassium tetrafluoroborate.
[0152] Grinding aids can be particularly useful in coated abrasive
and bonded abrasive products. In coated abrasive products, grinding
aid is typically used in the supersize coat, which is applied over
the surface of the abrasive particles. Sometimes, however, the
grinding aid is added to the size coat. Typically, the amount of
grinding aid incorporated into coated abrasive products are about
50-300 g/m.sup.2 (preferably, about 80-160 g/m.sup.2). In vitrified
bonded abrasive products grinding aid is typically impregnated into
the pores of the product.
[0153] The abrasive products can contain 100% fused abrasive
particles according to the present invention, or blends of such
abrasive particles with other abrasive particles and/or diluent
particles. However, at least about 2% by weight, preferably at
least about 5% by weight, and more preferably about 30-100% by
weight, of the abrasive particles in the abrasive products should
be abrasive particles according to the present invention. In some
instances, the abrasive particles according the present invention
may be blended with another abrasive particles and/or diluent
particles at a ratio between 5 to 75% by weight, about 25 to 75% by
weight about 40 to 60% by weight, or about 50% to 50% by weight
(i.e., in equal amounts by weight). Examples of suitable
conventional abrasive particles include fused aluminum oxide
(including white fused alumina, heat-treated aluminum oxide and
brown aluminum oxide), silicon carbide, boron carbide, titanium
carbide, diamond, cubic boron nitride, garnet, fused
alumina-zirconia, and sol-gel-derived abrasive particles, and the
like. The sol-gel-derived abrasive particles may be seeded or
non-seeded. Likewise, the sol-gel-derived abrasive particles may be
randomly shaped or have a shape associated with them, such as a rod
or a triangle. Examples of sol gel abrasive particles include those
described U.S. Pat. Nos. 4,314,827 (Leitheiser et al.), 4,518,397
(Leitheiser et al.), 4,623,364 (Cottringer et al.), 4,744,802
(Schwabel), 4,770,671 (Monroe et al.), 4,881,951 (Wood et al.),
5,011,508 (Wald et al.), 5,090,968 (Pellow), 5,139,978 (Wood),
5,201,916 (Berg et al.), 5,227,104 (Bauer), 5,366,523 (Rowenhorst
et al.), 5,429,647 (Larmie), 5,498,269 (Larmie), and 5,551,963
(Larmie), the disclosures of which are incorporated herein by
reference. Additional details concerning sintered alumina abrasive
particles made by using alumina powders as a raw material source
can also be found, for example, in U.S. Pat. Nos. 5,259,147 (Falz),
5,593,467 (Monroe), and 5,665,127 (Moltgen), the disclosures of
which are incorporated herein by reference. In some instances,
blends of abrasive particles may result in an abrasive article that
exhibits improved grinding performance in comparison with abrasive
articles comprising 100% of either type of abrasive particle.
[0154] If there is a blend of abrasive particles, the abrasive
particle types forming the blend may be of the same size.
Alternatively, the abrasive particle types may be of different
particle sizes. For example, the larger sized abrasive particles
may be abrasive particles according to the present invention, with
the smaller sized particles being another abrasive particle type.
Conversely, for example, the smaller sized abrasive particles may
be abrasive particles according to the present invention, with the
larger sized particles being another abrasive particle type.
[0155] Examples of suitable diluent particles include marble,
gypsum, flint, silica, iron oxide, aluminum silicate, glass
(including glass bubbles and glass beads), alumina bubbles, alumina
beads and diluent agglomerates. Fused abrasive particles according
to the present invention can also be combined in or with abrasive
agglomerates. Abrasive agglomerate particles typically comprise a
plurality of abrasive particles, a binder, and optional additives.
The binder may be organic and/or inorganic. Abrasive agglomerates
may be randomly shape or have a predetermined shape associated with
them. The shape may be a block, cylinder, pyramid, coin, square, or
the like. Abrasive agglomerate particles typically have particle
sizes ranging from about 100 to about 5000 micrometers, typically
about 250 to about 2500 micrometers. Additional details regarding
abrasive agglomerate particles may be found, for example, in U.S.
Pat. Nos. 4,311,489 (Kressner), 4,652,275 (Bloecher et al.),
4,799,939 (Bloecher et al.), 5,549,962 (Holmes et al.), and
5,975,988 (Christianson), the disclosures of which are incorporated
herein by reference.
[0156] The abrasive particles may be uniformly distributed in the
abrasive article or concentrated in selected areas or portions of
the abrasive article. For example, in a coated abrasive, there may
be two layers of abrasive particles. The first layer comprises
abrasive particles other than abrasive particles according to the
present invention, and the second (outermost) layer comprises
abrasive particles according to the present invention. Likewise in
a bonded abrasive, there may be two distinct sections of the
grinding wheel. The outermost section may comprise abrasive
particles according to the present invention, whereas the innermost
section does not. Alternatively, abrasive particles according to
the present invention may be uniformly distributed throughout the
bonded abrasive article.
[0157] Further details regarding coated abrasive products can be
found, for example, in U.S. Pat. Nos. 4,734,104 (Broberg),
4,737,163 (Larkey), 5,203,884 (Buchanan et al.), 5,152,917 (Pieper
et al.), 5,378,251 (Culler et al.), 5,417,726 (Stout et al.),
5,436,063 (Follett et al.), 5,496,386 (Broberg et al.), 5,609,706
(Benedict et al.), 5,520,711 (Helmin), 5,954,844 (Law et al.),
5,961,674 (Gagliardi et al.), and 5,975,988 (Christinason), the
disclosures of which are incorporated herein by reference. Further
details regarding bonded abrasive products can be found, for
example, in U.S. Pat. Nos. 4,453,107 (Rue), 4,741,743 (Narayanan et
al.), 4,800,685 (Haynes et al.), 4,898,597 (Hay et al.), 4,997,461
(Markhoff-Matheny et al.), 5,038,453 (Narayanan et al.), 5,110,332
(Narayanan et al.), and 5,863,308 (Qi et al.) the disclosures of
which are incorporated herein by reference. Further, details
regarding vitreous bonded abrasives can be found, for example, in
U.S. Pat. Nos. 4,543,107 (Rue), 4,898,597 (Hay), 4,997,461
(Markhoff-Matheny et al.), 5,094,672 (Giles et al.), 5,118,326
(Sheldon et al.), 5,131,926(Sheldon et al.), 5,203,886 (Sheldon et
al.), 5,282,875 (Wood et al.), 5,738,696 (Wu et al.), and 5,863,308
(Qi), the disclosures of which are incorporated herein by
reference. Further details regarding nonwoven abrasive products can
be found, for example, in U.S. Pat. No. 2,958,593 (Hoover et al.),
the disclosure of which is incorporated herein by reference.
[0158] Methods for abrading with abrasive particles according to
the present invention range from snagging (i.e., high pressure high
stock removal) to polishing (e.g., polishing medical implants with
coated abrasive belts), wherein the latter is typically done with
finer grades (e.g., less ANSI 220 and finer) of abrasive particles.
The abrasive particle may also be used in precision abrading
applications, such as grinding cam shafts with vitrified bonded
wheels. The size of the abrasive particles used for a particular
abrading application will be apparent to those skilled in the
art.
[0159] Abrading with abrasive particles according to the present
invention may be done dry or wet. For wet abrading, the liquid may
be introduced supplied in the form of a light mist to complete
flood. Examples of commonly used liquids include: water,
water-soluble oil, organic lubricant, and emulsions. The liquid may
serve to reduce the heat associated with abrading and/or act as a
lubricant. The liquid may contain minor amounts of additives such
as bactericide, antifoaming agents, and the like.
[0160] Abrasive particles according to the present invention may be
used to abrade workpieces such as aluminum metal, carbon steels,
mild steels, tool steels, stainless steel, hardened steel,
titanium, glass, ceramics, wood, wood like materials, paint,
painted surfaces, organic coated surfaces and the like. The applied
force during abrading typically ranges from about 1 to about 100
kilograms.
EXAMPLES
[0161] This invention is further illustrated by the following
examples, but the particular materials and amounts thereof recited
in these examples, as well as other conditions and details, should
not be construed to unduly limit this invention. Various
modifications and alterations of the present invention will become
apparent to those skilled in the art. All parts and percentages are
by weight unless otherwise indicated.
Example 1
[0162] A polyethylene bottle was charged with 187.2 grams of
alumina powder (obtained under the trade designation "APA-0.5" from
Condea Vista, Tucson, Ariz.), 112.9 grams of yttrium oxide powder
(obtained from H. C. Starck, Newton, Mass.), 0.6 gram of a
dispersing agent (obtained under the trade designation "DURAMAX
D-30005" from Rohm and Haas Company, Dear Park, Tex.), and 100.4
grams of distilled water. The powders were present in amounts to
provide 78.6 mole % Al.sub.2O.sub.3 and 21.4 mole % Y.sub.2O.sub.3.
About 450 grams of alumina milling media (10 mm diameter; 99.9%
alumina; obtained from Union Process, Akron, Ohio) were added to
the bottle, and the mixture was milled for 4 hours to thoroughly
mix the ingredients. After the milling, the milling media were
removed and the slurry was poured onto a glass ("PYREX") pan where
it was dried using a heat-gun held approximately 46 cm (18 inches)
above the pan. The pan was slowly oscillated while drying to
prevent the settling of the powder prior to complete drying. After
drying with the heat-gun, the pan was placed in a drying oven for
an additional 30 minutes at 90.degree. C. to more completely dry
the material. The dried powder bed was then scored with a spatula
and scraped from the-pan to form small flakes of material. Each
flake weighed about 0.5 to 3 grams. The flakes were calcined in air
by heating them to 670.degree. C. at rate of about 1.degree.
C./min., and then holding them at 670.degree. C. for 1 hour, after
which the power to the furnace power was shut-off, and the furnace
allowed to cool back to room temperature.
[0163] Several of the calcined flakes were melted in an arc
discharge furnace (Model No. 1-VAMF-20-22-45; from Advanced Vacuum
Systems, Ayer, Mass.). About 15 grams of the calcined flakes were
placed on the chilled copper plate located inside a furnace
chamber. The furnace chamber was evacuated and then backfilled with
Argon gas at a 260 torr pressure. An arc was struck between an
electrode and a plate. The temperatures generated by the arc
discharge were high enough to quickly melt the calcined flakes.
After melting was complete, the material was maintained in a molten
state for about 30 seconds to homogenize the melt. The resultant
melt was rapidly cooled by shutting off the arc and allowing the
melt to cool on its own. Rapid cooling was ensured by small mass of
a sample and a large heat sinking capability of a chilled copper
plate. The fused material was removed from the furnace within one
minute after the power to the furnace was turned off. Although not
wanting to be bound by theory, it is estimated that the cooling
rate of the melt on the surface of the water chilled copper plate
was 1500.degree. C./min. The fused material was white-green in
color.
[0164] FIG. 8 is a scanning electron microscope (SEM)
photomicrograph of a polished section of fused Example 1 material.
The polished section was prepared using conventional mounting and
polishing techniques. Polishing was done using a polisher (obtained
from Buehler of Lake Bluff, Ill. under the trade designation
"ECOMET 3 TYPE POLISHER-GRINDER"). The sample was polished for
about 3 minutes with a diamond wheel, followed by three minutes of
polishing with each of 45, 30, 15, 9, and 3 micrometer diamond
slurries. The polished sample was coated with a thin layer of
gold-palladium and viewed using JEOL SEM (Model JSM 840A).
Referring again to FIG. 8, the photomicrograph shows a
cutectic-derived microstructure comprising a plurality of colonies.
The colonies were about 10-40 micrometers in size. Based on powder
x-ray diffraction of a portion of Example 1 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline Y.sub.3Al.sub.5O.sub.12, and the dark portions
.alpha.-Al.sub.2O.sub.3. The widths of these phases observed in the
polished section were up to about 1 micrometer.
[0165] Example 1 fused material was crushed by using a "Chipmunk"
jaw crusher (Type VD, manufactured by BICO Inc., Burbank, Calif.)
into (abrasive) particles and graded to retain the -25+30 and
-30+35 mesh fractions (USA Standard Testing Sieves). These two mesh
fractions were combined to provide a 50/50 blend. Thirty grams of
the 50/50 blend of -25+30 and -30+35 mesh fractions were
incorporated into a coated abrasive disc. The coated abrasive disc
was made according to conventional procedures. The fused abrasive
particles were bonded to 17.8 cm diameter, 0.8 mm thick vulcanized
fiber backings (having a 2.2 cm diameter center hole) using a
conventional calcium carbonate-filled phenolic make resin (48%
resole phenolic resin, 52% calcium carbonate, diluted to 81% solids
with water and glycol ether) and a conventional cryolite-filled
phenolic size resin (32% resole phenolic resin, 2% iron oxide, 66%
cryolite, diluted to 78% solids with water and glycol ether). The
wet make resin weight was about 185 g/m.sup.2. Immediately after
the make coat was applied, the fused abrasive particles were
electrostatically coated. The make resin was precured for 120
minutes at 88.degree. C. Then the cryolite-filled phenolic size
coat was coated over the make coat and abrasive particles. The wet
size weight was about 850 g/m.sup.2. The size resin was cured for
12 hours at 99.degree. C. The coated abrasive disc was flexed prior
to testing.
[0166] The average microhardnesses of Example 1 abrasive particles
were measured by mounting loose abrasive particles (about 10 mesh
in size) in mounting resin (obtained under the trade designation
"EPOMET" from Buehler Ltd., Lake Bluff, Ill.). The resulting
cylinder of resin was about 2.5 cm (1 inch) in diameter and about
1.9 cm (0.75 inch) tall. The mounted samples were polished using a
conventional grinder/polisher (obtained under the trade designation
"EPOMET" from Buehler Ltd.) and conventional diamond slurries with
the final polishing step using a 1 micrometer diamond slurry
(obtained under the trade designation "METADI" from Buehler Ltd.)
to obtain polished cross-sections of the sample.
[0167] The microhardness measurements were made using a
conventional microhardness tester (obtained under the trade
designation "MITUTOYO MVK-VL" from Mitutoyo Corporation, Tokyo,
Japan) fitted with a Vickers indenter using a 500-gram indent load.
The microhardness measurements were made according to the
guidelines stated in ASTM Test Method E384 Test Methods for
Microhardness of Materials (1991), the disclosure of which is
incorporated herein by reference. The microhardness values were an
average of 20 measurements. The average microhardness was 16.2
GPa.
[0168] Several Example 1 abrasive particles were heated placed in a
platinum crucible and heated to 1000.degree. C. at 50.degree.
C./hour, held at 1000.degree. C. for 4 hours (in air), and then
cooled to room temperature at about 100.degree. C./hour. The color
of the abrasive particles after heating was the same as before
heating (i.e., white-green). The average microhardness of the
abrasive particles after heating was 16.1 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed after heating was substantially the same as
the microstructure observed before heating.
[0169] Several Example 1 abrasive particles were also heated placed
in a platinum crucible and heated to 1000.degree. C. at 50.degree.
C./hour, held at 1000.degree. C. for 8 hours (in air), and then
cooled to room temperature at about 100C./hour. The color of the
abrasive particles after heating was the same as before heating
(i.e., white-green). The average microhardness of the abrasive
particles after heating was 16.0 GPa. The polished cross-sections
prepared for the microhardness measurements were examined using the
SEM in the secondary electron mode. The microstructure observed
after heating was substantially the same as the microstructure
observed before heating.
Comparative Example A
[0170] The Comparative Example A coated abrasive disc was prepared
as described in Example 1 except heat-treated fused alumina
abrasive particles (obtained under the trade designation "ALODUR
BFRPL"" from Triebacher, Villach, Austria) was used in place of the
Example 1 fused abrasive particles.
Comparative Example B
[0171] The Comparative Example B coated abrasive disc was prepared
as described in Example 1 except alumina-zirconia abrasive
particles (having a eutectic composition of 53% Al.sub.2O.sub.3 and
47% ZrO.sub.2; obtained under the trade designation "NORZON" from
Norton Company, Worcester, Mass.) was used in place of the Example
1 fused abrasive particles.
[0172] The average microhardness of Comparative Example B abrasive
particles was determined, as described above in Example 1, to be
16.0 GPa. The color of the Comparative Example B abrasive particles
was gray-navy blue.
[0173] Several Comparative Example B abrasive particles were heated
placed in a platinum crucible and heated to 1000.degree. C. at
50.degree. C./hour, held at 1000.degree. C. for 4 hours (in air),
and then cooled to room temperature at about 100.degree. C./hour.
The color of the abrasive particles after heating was beige. The
average microhardness of the abrasive particles after heating was
12.9 GPa. The polished cross-sections prepared for the
microhardness measurements were examined using the SEM in the
secondary electron mode. An SEM photomicrograph a Comparative
Example B abrasive particle before heating is shown in FIG. 11. An
SEM photomicrograph a Comparative Example B abrasive particle after
heating is shown in FIG. 12. The microstructure observed after
heating was different than that observed before heating. The
differences were observed most predominately at the colony
boundaries.
[0174] Further powder x-ray diffraction (using a Phillips XRG 3100
x-ray diffractometer with copper K al radiation of 1.54050
Angstrom) was used to qualitatively measure the phases present in
Comparative Example B abrasive particles before and after the above
described heat-treatment by comparing the peak intensities of 111
of cubic and/or tetragonal reflection at about 2.theta.=30 degrees,
to that of 111 of monoclinic reflection at about 2.theta.=28
degrees. For reference see "Phase Analysis in Zirconia Systems,"
Garvie, R. C. and Nicholson, P. S., Journal of the American Ceramic
Society, vol 55 (6), pp. 303-305, 1972, the disclosure of which is
incorporated herein by reference. The samples were ground and -120
mesh powders used for analysis. The unheat-treated Comparative
Example B abrasive particles contained both the monoclinic and
cubic and/or tetragonal zirconia phases. For the heat-treated
sample, a decrease in the cubic and/or tetragonal phase content
with a corresponding increase in monoclinic phase content was
observed.
[0175] Several Comparative Example B abrasive particles were heated
placed in a platinum crucible and heated to 1000.degree. C. at
50.degree. C./hour, held at 1000.degree. C. for 8 hours (in air),
and then cooled to room temperature at about 100.degree. C./hour.
The color of the abrasive particles after heating was beige. The
average microhardness of the abrasive particles after heating was
12.8 GPa. The polished cross-sections prepared for the
microhardness measurements were examined using the SEM in the
secondary electron mode. An SEM photomicrograph a Comparative
Example B abrasive particle after heating is shown in FIG. 13. The
microstructure observed after heating was different than that
observed before heating. The differences, which were greater than
those observed for the heat-treatment at 1000.degree. C. for 4
hours, were again observed most predominately at the colony
boundaries.
[0176] The effect of two vitrified bonding materials on Comparative
Example B abrasive particles were evaluated as follows. A first
vitrified bond material was prepared by charging a plastic jar (4
3/8 inches (11 .1 cm) in diameter; 4 3/8 inches (11.1 cm) in
height) with 70 parts of a glass frit (37.9% SiO.sub.2, 28.5%
B.sub.2O.sub.3, 15.6% Al.sub.2O.sub.3, 13.9% Na.sub.2O, and 4.1%
K.sub.2O; obtained under the trade designation "FERRO FRIT 3227"
from Ferro Corporation, Cleveland, Ohio), 27 parts of Kentucky Ball
Clay (No 6DC; obtained from Old Hickory Clay Company, Hickory,
Ky.), 3.5 parts of Li.sub.2CO.sub.3 (obtained from Alfa Aesar
Chemical Company, Ward Hill, Mass.), 3 parts CaSiO.sub.3 (obtained
from Alfa Aesar Chemical Company), and 625 grams of 1.3 cm (0.5
inch) diameter plastic coated steel media, and then dry milling the
contents at 90 rpm for 7 hours. The composition was formulated to
provide a vitrified bond material comprising about 45% SiO.sub.2,
about 19% Al.sub.2O.sub.3, about 20% B.sub.2O.sub.3, about 10%
Na.sub.2O, about 3% K.sub.2O, about 1.5% Li.sub.2O, and about 1.5%
CaO. The dry milled material and Comparative Example B abrasive
particles were pressed into a 3.2 cm.times.0.6 cm (1.25
inch.times.0.25 inch) pellet. The pellet was heated to 1000.degree.
C. at 50.degree. C./hour, held at 1000.degree. C. for 8 hours (in
air), and then cooled to room temperature at about 100.degree.
C./hour. The pellet was prepared by mixing, in order, 20 parts of
Comparative Example B abrasive particles (-20+30 mesh), 0.24 part
of hydrolyzed starch (obtained under the trade designation
"DEXTRIN" from Aldrich Chemical Company, Milwaukee, Wis.), 0.02
part glycerine (obtained from Aldrich Chemical Company), 0.72 part
water, 3.14 parts of the dry milled material, and 0.4 part of
hydrolyzed starch ("DEXTRIN"). The pellet was pressed under a load
of 2273 kilograms (5000 lbs.). The average microhardness of the
abrasive particles after heating in the vitrified bonding material
was 13.6 GPa, although some of the Comparative Example B abrasive
particles exhibit such severe degradation that microhardness
measurements could not be effectively made (portions of the
particles were too weak). There was variability in the color of the
heat-treated abrasive particles, although the majority of the
particles were beige. The polished cross-sections prepared for the
microhardness measurements were examined using the SEM in the
secondary electron mode. An SEM photomicrograph a Comparative
Example B abrasive particle after heating is shown in FIG. 14. The
microstructure observed after heating was different than that
observed before heating. The differences, which were greater than
those observed for the heat-treatment at 1000.degree. C. for 4
hours, were again observed most predominately at the colony
boundaries.
[0177] A second vitrified bond material was prepared by charging a
plastic jar (4 3/8 inches (11.1 cm) in diameter; 4 3/8 inches (11.1
cm) in height) with 45 parts of Kentucky Ball Clay (No. 6DC;
obtained from Old Hickory Clay Company), 28 parts of anhydrous
sodium tetraborate (obtained from Alfa Aesar Chemical Company), 25
parts of feldspar (obtained under the trade designation"G-200
Feldspar" from Feldspar Corporation, Atlanta, Ga.), 3.5 parts of
Li.sub.2CO.sub.3 (obtained from Alfa Aesar Chemical Company), 2.5
parts of CaSiO.sub.3 (obtained from Alfa Aesar Chemical Company),
and 625 grams of 1.3 cm (0.5 inch) diameter plastic coated steel
media, and then dry milling the contents at 90 rpm for 7 hours. The
composition was formulated to provide a vitrified bond material
comprising about 45% SiO.sub.2, about 19% Al.sub.2O.sub.3, about
20% B.sub.2O.sub.3, about 10% Na.sub.2O, about 3% K.sub.2O, about
1.5% Li.sub.2O, and about 1.5% CaO. The dry milled material and
Comparative Example B abrasive particles were pressed into a 3.2
cm.times.0.6 cm (1.25 inch.times.0.25 inch) pellet. The pellet was
heated to 1000.degree. C. at 50.degree. C./hour, held at
1000.degree. C. for 8 hours (in air), and then cooled to room
temperature at about 100.degree. C./hour. The pellet was prepared
by mixing, in order, 20 parts of Comparative Example B abrasive
particles (-20+30 mesh), 0.24 part of hydrolyzed starch
("DEXTRIN"), 0.02 part glycerine (obtained from Aldrich Chemical
Company), 0.72 part water, 3.14 parts of the dry milled material,
and 0.4 part of hydrolyzed starch ("DEXTRIN"). The pellet was
pressed under a load of 2273 kilograms (5000 lbs.). The average
microhardness of the abrasive particles after heating in the
vitrified bonding material was 13.4 GPa, although some of the
Comparative Example B abrasive particles exhibit such severe
degradation that microhardness measurements could not be
effectively made (portions of the particles were too weak). There
was variability in the color of the heat-treated abrasive
particles, although the majority of the particles were beige. The
polished cross-sections prepared for the microhardness measurements
were examined using the SEM in the secondary electron mode. The
microstructure observed after heating was different than that
observed before heating. The differences, which were greater than
those observed for the heat-treatment at 1000.degree. C. for 4
hours, were again observed most predominately at the colony
boundaries.
Comparative Example C
[0178] The Comparative Example C coated abrasive disc was prepared
as described in Example 1 except sol-gel-derived abrasive particles
(commercially available under the trade designation "321 CUBITRON"
from the 3M Company, St. Paul, Minn.) was used in place of the
Example 1 fused abrasive particles.
Grinding Performance of Example 1 and Comparative Examples A-C
[0179] The grinding performance of Example 1 and Comparative
Examples A-C coated abrasive discs were evaluated as follows. Each
coated abrasive disc was mounted on a beveled aluminum back-up pad,
and used to grind the face of a pre-weighed 1.25 cm.times.18
cm.times.10 cm 1018 mild steel workpiece. The disc was driven at
5,000 rpm while the portion of the disc overlaying the beveled edge
of the back-up pad contacted the workpiece at a load of 8.6
kilograms. Each disc was used to grind individual workpiece in
sequence for one-minute intervals. The total cut was the sum of the
amount of material removed from the workpieces throughout the test
period. The total cut by each sample after 12 minutes of grinding
as well as the cut at 12th minute (i.e., the final cut) are
reported in Table 1, below.
1TABLE 1 Example Total cut, g Final cut, g Comp. A 418 23 Comp. B
621 48 Comp. C 859 75 1 732 56
Example 2
[0180] Example 2 fused material and abrasive particles were
prepared as described in Example 1, except (a) the polyethylene
bottle was charged with 173 grams of alumina powder ("APA-0.5"),
19.3 grams of magnesium oxide powder (obtained under the trade
designation "MAGCHEM 10-325" from Martin Marietta Magnesia
Specialties, Hunt Valley, Md.), 107.8 grams of yttrium oxide powder
obtained from H. C. Starck, Newton, Mass.), 0.6 gram of a
dispersing agent ("DURAMAX D-30005"), and 137.4 grams of distilled
water, and (b) the powders were present in amounts to provide 64
mole % Al.sub.2O.sub.3, 18 mole % MgO, and 18 mole %
Y.sub.2O.sub.3. The fused material was white in color.
[0181] FIG. 9 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 2 material. The photomicrograph shows a
eutectic-derived microstructure comprising a plurality of colonies.
The colonies are about 10-40 micrometers in size. Based on powder
x-ray diffraction of a portion of Example 2 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline Y.sub.3Al.sub.5O.sub.12, and the dark portions a
crystalline Al.sub.2O.sub.3-rich spinel solid solution phase. The
width of these phases observed in the polished section were up to
about 1 micrometer.
Comparative Example D
[0182] Comparative Example D fused material and abrasive particles
were prepared as described in Example 1, except (a) the
polyethylene bottle was charged with 149.5 grams of alumina powder
("APA-0.5"), 149.4 grams of yttria-stabilized zirconia oxide powder
(with a nominal composition of 94 wt % ZrO.sub.2 (+HfO.sub.2) and
5.4 wt % Y.sub.2O.sub.3; obtained under the trade designation "HSY
3.0" from Zirconia Sales, Inc. of Marietta, Ga.), 0.6 gram of a
dispersing agent ("DURAMAX D-30005"), and 136.5 grams of distilled
water, and (b) the powders were present in amounts to provide 54.8
mole % Al.sub.2O.sub.3 and 45.2 mole % ZrO.sub.2. The fused
material was white in color.
[0183] FIG. 10 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Comparative Example D material. The
photomicrograph shows a eutectic derived microstructure comprising
a plurality of colonies. The colonies were about 5-40 micrometers
in size. Based on powder x-ray diffraction of a portion of
Comparative Example D material, and examination of the polished
sample using SEM in the backscattered mode, it is believed that the
white portions in the photomicrograph were crystalline ZrO.sub.2,
and the dark portions .alpha.-Al.sub.2O.sub.3. The widths of these
phases observed in the polished section were up to about 0.5
micrometer.
[0184] The average microhardness of Comparative Example D was
determined, as described above in Example 1, to be 15.3 GPa.
[0185] Several Comparative Example D particles were heated placed
in a platinum crucible and heated to 1000.degree. C. at 50.degree.
C./hour, held at 1000.degree. C. for 4 hours (in air), and then
cooled to room temperature at about 100.degree. C./hour. The color
of the abrasive particles after heating was white. The average
microhardness of the abrasive particles after heating was 15.0 GPa.
The polished cross-sections prepared for the microhardness
measurements were examined using the SEM in the secondary electron
mode. An SEM photomicrograph Comparative Example D material before
heating is shown in FIG. 15. The microstructure observed after
heating was substantially the same as the microstructure observed
before heating.
[0186] Further powder x-ray diffraction, as described above for
Comparative Example B, was used to qualitatively measure the phases
present in Comparative Example D material before and after the
above described heat-treatment by comparing the peak intensities of
111 of cubic and/or tetragonal reflection at about 2.theta.=30
degrees, to that of 111 of monoclinic reflection at about
2.theta.=28 degrees. The unheat-treated Comparative Example D
material contained predominantly cubic and/or tetragonal zirconia
before and after the heat-treatment (i.e., there was no significant
difference noted in the x-ray diffraction results).
[0187] Several Comparative Example D particles were also heated
placed in a platinum crucible and heated to 1000.degree. C. at
50.degree. C./hour, held at 1000.degree. C. for 8 hours (in air),
and then cooled to room temperature at about 100.degree. C./hour.
The color of the abrasive particles after heating was white. The
average microhardness of the abrasive particles after heating was
15.0 GPa. The polished cross-sections prepared for the
microhardness measurements were examined using the SEM in the
secondary electron mode. The microstructure observed after heating
was only slightly different than that observed before heating. An
SEM photomicrograph Comparative Example D after heating is shown in
FIG. 16. There was some cracks observed in the heat-treated
material, generally near primary crystals of ZrO.sub.2.
Differential Thermal Analysis (DTA) And Thermogravimetric Analysis
(TGA) of Example 1 and Comparative Example B and D Abrasive
Particles/Materials
[0188] Differential thermal analysis (DTA) and thermogravimetric
analysis (TGA) were conducted for each of Example 1 and Comparative
Example B and D abrasive particles/materials. Each material was
crushed with a mortar and pestle and screened to retain particles
that were in the 400-500 micrometer size range.
[0189] DTA/TGA runs were made (using an instrument obtained from
Netzsch Instruments, Selb, Germany under the trade designation
"NETZSCH STA 409 DTA/TGA") for each of the screened samples. The
amount of each screened sample placed in the 100 microliter
Al.sub.2O.sub.3 sample holder was 129.5 micrograms (Example 1),
125.8 micrograms (Comparative Example D), 127.3 micrograms
(Comparative Example B), respectively. Each sample was heated in
static air at a rate of 10.degree. C./minute from room temperature
(about 25.degree. C.) to 1300.degree. C.
[0190] Referring to FIG. 5, line 157 is the plotted DTA data for
the Example 1 material; line 159, the plotted TGA data. Referring
to FIG. 6, line 177 is the plotted DTA data for the Comparative
Example D material; line 179, the plotted TGA data. Referring to
FIG. 7, line 187 is the plotted DTA data for the Comparative
Example B material; line 189, the plotted TGA data. The change in
weight of the sample through the TGA run was, for Example 1, 0.22%;
for Comparative Example D, 0.73%; and, for Comparative Example B,
1.16%.
Example 3
[0191] Example 3 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 171.6
grams of alumina powder ("APA-0.5"), 83.4 grams of yttrium oxide
powder (obtained from H. C. Starck, Newton, Mass.), 45 grams of
zirconium oxide powder (with a nominal composition of 100 wt %
ZrO.sub.2 (+HfO.sub.2); obtained under the trade designation "DK-2"
from Zirconia Sales, Inc. of Marietta, Ga.), 0.6 gram of a
dispersing agent ("DURAMAX D-30005"), and 100 grams of distilled
water. The fused material was white-red in color.
[0192] FIGS. 17 and 18 are scanning electron microscope (SEM)
photomicrographs of a polished section (prepared as described in
Example 1) of fused Example 3 material. Referring to FIGS. 17 and
18, the photomicrograph shows a eutectic-derived microstructure
comprising a plurality of colonies. The colonies were about 5-30
micrometers in size. Based on powder x-ray diffraction of a portion
of Example 3 material, and examination of the polished sample using
SEM in the backscattered mode, it is believed that the white
portions in the photomicrograph were crystalline cubic ZrO.sub.2,
the gray portions crystalline Y.sub.3Al.sub.5O.sub.12, and the dark
portions .alpha.-Al.sub.2O.sub.3. The widths of these phases
observed in the polished section were up to about 3 micrometers.
Eutectic phases making up the colonies were in a lamellar
arrangement. The alumina phases were seen as crystals exhibiting a
trigonal shape. The orientation of at least a portion of the
lamellar (i.e. orientation of eutectic crystallization) was
observed to follow the orientation of the alumina in trigonal
outline which was evident by an approximately 120 degree angle at
which adjacent lamellar run into each other. While not wishing to
be bounded by theory, it is believed that during crystallization of
the melt of a composition at or near ternary eutectic, primary
alumina crystallized first as a seed in a trigonal shape. The
consequent coupled growth of eutectic in the form of lamellar
followed, at least initially, the orientation of the seed. A
eutectic colony then included alumina seeds of the same orientation
(or a single seed) together with the eutectic lamellar growth.
Further, it was observed that the colony boundaries did not exhibit
phase coarsening as was observed in the binary eutectic (manifested
by the significant coarsening of crystals of eutectic phases in an
immediate vicinity of colony boundary) of Example 1.
[0193] The average microhardness of Example 3 was determined, as
described above in Example 1, to be 16.5 GPa.
[0194] Several Example 3 particles were heated placed in a platinum
crucible and heated to 1000.degree. C. at 50.degree. C./hour, held
at 1000.degree. C. for 8 hours (in air), and then cooled to room
temperature at about 100.degree. C./hour. The color of the abrasive
particles after heating was white. The average microhardness of the
Example 3 particles after heating was 16.7 GPa.
Grinding Performance of Example 3 and Comparative Examples A-C
[0195] The grinding performance of Example 3 and Comparative
Examples A-C coated abrasive discs were evaluated as described
above for Example 1 and Comparative Examples A-C. The results are
reported in Table 2, below.
2TABLE 2 Example Total cut, g Final cut, g Comp. A 424 24 Comp. B
614 45 Comp. C 940 79 3 711 58
Example 4
[0196] Example 4 fused material and abrasive particles were
prepared as described in Example 1, except the polyethylene bottle
was charged with 181.7 grams of alumina powder ("APA-0.5"), 88.3
grams of yttrium oxide powder (obtained from H. C. Starck, Newton,
Mass.), 30 grams of zirconium oxide powder ("DK-2"), 0.6 gram of a
dispersing agent ("DURAMAX D-30005"), and 100 grams of distilled
water.
[0197] FIG. 19 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 4 material. Referring to FIG. 19, the
photomicrograph shows a ternary eutectic-derived microstructure
comprising a plurality of colonies. The colonies were about 10-40
micrometers in size. Based on powder x-ray diffraction of a portion
of Example 4 material, and examination of the polished sample using
SEM in the backscattered mode, it is believed that the white
portions in the photomicrograph were crystalline cubic ZrO.sub.2,
the gray portions crystalline Y.sub.3Al.sub.5O.sub.12, and the dark
portions .alpha.-Al.sub.2O.sub.3. The widths of these phases
observed in the polished section were up to about 5 micrometer.
Further, large primary crystals (believed to be Al.sub.2O.sub.3 and
Y.sub.3Al.sub.5O.sub.12), present in the form of dendrites, were
observed in some areas of the polished cross-section, indicating
possible deviation of the composition from an exact eutectic
composition.
Example 5
[0198] Example 5 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 141.3
grams of alumina powder ("APA-0.5"), 68.7 grams of yttrium oxide
powder (obtained from H. C. Starck, Newton, Mass.), 90 grams of
zirconium oxide powder ("DK-2"), 0.6 gram of a dispersing agent
("DURAMAX D-30005"), and 100 grams of distilled water.
[0199] FIG. 20 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 5 material. Referring to FIG. 20, the
photomicrograph shows a ternary eutectic-derived microstructure
comprising a plurality of colonies. The colonies were about 10-40
micrometers in size. Based on powder x-ray diffraction of a portion
of Example 5 material, and examination of the polished sample using
SEM in the backscattered mode, it is believed that the white
portions in the photomicrograph were crystalline cubic ZrO.sub.2,
the gray portions crystalline Y.sub.3Al.sub.5O.sub.12, and the dark
portions .alpha.-Al.sub.2O.sub.3. The widths of these phases
observed in the polished section were up to about 5 micrometers.
Further, large primary crystals (believed to be ZrO.sub.2), present
in the form of dendrites, were observed in some areas of the
polished cross-section, indicating possible deviation of the
composition from an exact eutectic composition.
Example 6
[0200] Example 6 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 191.8
grams of alumina powder ("APA-0.5"), 93.2 grams of yttrium oxide
powder (obtained from H. C. Starck, Newton, Mass.), 15 grams of
zirconium oxide powder ("DK-2"), 0.6 gram of a dispersing agent
("DURAMAX D-30005"), and 100 grams of distilled water.
[0201] FIG. 21 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 6 material. Referring to FIG. 21, the
photomicrograph shows a binary eutectic-derived microstructure.
Based on powder x-ray diffraction of a portion of Example 6
material, and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline cubic ZrO.sub.2, the gray portions
crystalline Y.sub.3Al.sub.5O.sub.12, and the dark portions
.alpha.-Al.sub.2O.sub.3. The widths of these phases observed in the
polished section were up to about 10 micrometers. Further, large
primary crystals (believed to be ZrO.sub.2) where observed between
crystals of Al.sub.2O.sub.3 and Y.sub.3Al.sub.5O.sub.12, indicating
that deviation of the composition from an exact eutectic
composition is quite large.
Example 7
[0202] Example 7 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 201.9
grams of alumina powder ("APA-0.5"), 88.3 grams of yttrium oxide
powder (obtained from H. C. Starck, Newton, Mass.), 9.8 grams of
neodymium oxide powder (obtained from Molycorp, Inc., Brea,
Calif.), 0.6 gram of a dispersing agent ("DURAMAX D-30005"), and
100 grams of distilled water.
[0203] FIG. 22 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 7 material. Referring to FIG. 22, the
photomicrograph shows a eutectic-derived microstructure. Based on
powder x-ray diffraction of a portion of Example 7 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were Nd-rich phase, the gray portions crystalline yttrium aluminum
garnet with some yttrium substituted by neodymium, and the dark
portions .alpha.-Al.sub.2O.sub.3. The widths of these phases
observed in the polished section were up to about 10
micrometers.
Example 8
[0204] Example 8 fused material was prepared as described in
Example 1, except (a) the polyethylene bottle was charged with
201.9 grams of alumina powder ("APA-0.5") and 98.1 grams of yttrium
oxide powder (obtained from H. C. Starck, Newton, Mass.), and (b)
the powders were present in amounts to provide 82 mole %
Al.sub.2O.sub.3 and 18 mole % Y.sub.2O.sub.3.
[0205] FIG. 23 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 8 material. The photomicrograph shows a
eutectic-derived microstructure comprising a plurality of colonies.
The colonies were about 10-40 micrometers in size. Based on powder
x-ray diffraction of a portion of Example 8 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline Y.sub.3Al.sub.5O.sub.12, and the dark portions
.alpha.-Al.sub.2O.sub.3. The widths of these phases observed in the
polished section were up to about 1 micrometer.
Grinding Performance of Example 8 and Comparative Examples A-C
[0206] The grinding performance of Example 8 and Comparative
Examples A-C coated abrasive discs were evaluated as described
above for Example 1 and Comparative Examples A-C. The results are
reported in Table 3, below.
3TABLE 3 Example Total cut, g Final cut, g Comp. A 431 25 Comp. B
674 50 Comp. C 933 78 8 787 56
Example 9
[0207] Example 9 fused material, abrasive particles, and discs were
prepared as described in Example 1, except (a) the polyethylene
bottle was charged with 242.5 grams of alumina powder ("APA-0.5"),
257.5 grams of gadolinium oxide powder. (obtained from Molycorp,
Inc., Brea, Calif.), 0.6 gram of a dispersing agent ("DURAMAX
D-30005"), and 150.6 grams of distilled water, and (b) the powders
were present in amounts to provide 77 mole % Al.sub.2O.sub.3 and 23
mole % Gd.sub.2O.sub.3. The fused material was white-yellow in
color.
[0208] FIG. 24 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 9 material. The photomicrograph shows a
eutectic-derived microstructure comprising a plurality of colonies.
The colonies were about 5-20 micrometers in size. Based on powder
x-ray diffraction of a portion of Example 9 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline GdAlO.sub.3, and the dark portions
.alpha.-Al.sub.2O.sub.3. The widths of these phases observed in the
polished section were up to about 0.7 micrometer. It is also noted
that there were many pores observed in the fused material.
Example 10
[0209] Example 10 fused material, abrasive particles, and discs
were prepared as described in Example 1, except (a) the
polyethylene bottle was charged with 145.6 grams of alumina powder
("APA-0.5"), 151.2 grams of lanthanum oxide powder (obtained from
Molycorp, Inc., Brea, Calif.), 0.6 gram of a dispersing agent
("DURAMAX D-30005"), and 129.5 grams of distilled water, and (b)
the powders were present in amounts to provide 75 mole %
Al.sub.2O.sub.3 and 25 mole % La2O.sub.3. The fused material was
white-red in color; although some of the abrasive particles were
redder than others.
[0210] FIG. 25 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 10 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-30 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 10 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline LaAlO.sub.3, and the dark portions
crystalline LaAl.sub.11O.sub.18. The widths of these phases
observed in the polished section were up to about 0.5 micrometer.
Further, large primary crystals (believed to be LaAlO.sub.3),
present in the form of dendrites, were observed in some areas of
the polished cross-section, indicating possible deviation of the
composition from an exact eutectic composition toward a
La.sub.2O.sub.3 rich composition.
[0211] The average microhardness of Example 10 abrasive particles
was determined, as described above in Example 1, except Example 10,
11, and 12 abrasive particles (i.e., Example 10, 11, and 12
abrasive particles were mixed together; but were distinguishable
from each other visually based on color, and under SEM based on
composition) were incorporated into the pellet. The average
microhardness of Example 10 abrasive particles was 15.0 GPa.
[0212] Differential thermal analysis (DTA) and thermogravimetric
analysis (TGA) were conducted for Example 10 material as described
for of Example 1 and Comparative Example B and D abrasive
particles/materials. Referring to FIG. 31, line 167 is the plotted
DTA data for the Example 10 material; line 169, the plotted TGA
data. The change in weight of the sample through the TGA run was
0.22%.
[0213] Several Example 10 abrasive particles (together with Example
11 and 12abrasive particles) were heated placed in a platinum
crucible and heated to 1000.degree. C. at 50.degree. C./hour, held
at 1000.degree. C. for 4 hours (in air), and then cooled to room
temperature at about 100.degree. C./hour. The color of the Example
10 abrasive particles after heating was the same as before heating
(i.e., white-red). The average microhardness of the Example 10
abrasive particles after heating was 14.1 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed for the Example 10 abrasive particles after
heating was substantially the same as the microstructure observed
before heating.
[0214] Several Example 10 abrasive particles (together with Example
11 and 12 abrasive particles) were also heated placed in a platinum
crucible and heated to 1000.degree. C. at 50.degree. C./hour, held
at 1000.degree. C. for 8 hours (in air), and then cooled to room
temperature at about 100.degree. C./hour. The color of the Example
10 abrasive particles after heating was the same as before heating
(i.e., white-red). The average microhardness of the Example 10
abrasive particles after heating was 14.3 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed for the Example 10 abrasive particles after
heating was substantially the same as the microstructure observed
before heating.
[0215] The effect of two vitrified bonding materials on Example 10
abrasive particles were evaluated as described for Comparative
Example B, except Example 10, 11, and 12 abrasive particles (i.e.,
Example 10, 11, and 12 abrasive particles were mixed together; but
were distinguishable from each other visually based on color, and
under SEM based on composition) were incorporated into the pellets.
The polished cross-sections were examined using the SEM in the
secondary electron mode. The microstructure observed after heating
was substantially the same as the microstructure observed before
heating. The color of the Example 10 abrasive particles after
heating with the vitrified bonding material was the same as before
heating (i.e., white-red).
Example 11
[0216] Example 11 fused material, abrasive particles, and discs
were prepared as described in Example 1, except (a) the
polyethylene bottle was charged with 143.6 grams of alumina powder
("APA-0.5"), 147.6 grams of neodymium oxide powder (obtained from
Molycorp, Inc., Brea, Calif.), 0.6 gram of a dispersing agent
("DURAMAX D-30005"), and 138.5 grams of distilled water, and (b)
the powders were present in amounts to provide 75 mole %
Al.sub.2O.sub.3 and 25 mole % Nd.sub.2O.sub.3. The fused material
was white-blue in color; although some of the abrasive particles
were bluer than others.
[0217] FIG. 26 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 11 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 10-40 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 11 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline NdAlO.sub.3, and the dark portions
crystalline NdAl.sub.11O.sub.18. The widths of these phases
observed in the polished section were up to about 0.5 micrometer.
Further, large primary crystals (believed to be NdAlO.sub.3),
present in the form of dendrites, were observed in some areas of
the polished cross-section, indicating possible deviation of the
composition from an exact eutectic composition toward a
Nd.sub.2O.sub.3 rich composition.
[0218] The average microhardness of Example 11 abrasive particles
was determined, as described above in Example 1, except Example 10,
11, and 12 abrasive particles (i.e., Example 10, 11, and 12
abrasive particles were mixed together; but were distinguishable
from each other visually based on color, and under SEM based on
composition) were incorporated into the pellet. The average
microhardness of Example 11 abrasive particles was to be 14.5
GPa.
[0219] Several Example 11 abrasive particles (together with Example
10 and 12 abrasive particles) were heated placed in a platinum
crucible and heated to 1000.degree. C. at 50.degree. C./hour, held
at 1000.degree. C. for 4 hours (in air), and then cooled to room
temperature at about 100.degree. C./hour. The color of the Example
11 abrasive particles after heating was the same as before heating
(i.e., white-blue). The average microhardness of the Example 11
abrasive particles after heating was 14.1 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed for the Example 1 abrasive particles after
heating was substantially the same as the microstructure observed
before heating.
[0220] Several Example 11 abrasive particles (together with Example
10 and 12 abrasive particles) were also heated placed in a platinum
crucible and heated to 1000.degree. C. at 50.degree. C./hour, held
at 1000.degree. C. for 8 hours (in air), and then cooled to room
temperature at about 100C./hour. The color of the Example 11
abrasive particles after heating was the same as before heating
(i.e., white-blue). The average microhardness of the Example 11
abrasive particles after heating was 14.5 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed for the Example 11 abrasive particles after
heating was substantially the same as the microstructure observed
before heating.
[0221] The effect of two vitrified bonding materials on Example 11
abrasive articles were evaluated as described in Comparative
Example B, except 10, 11, and 12 abrasive particles (i.e., Example
10, 11, and 12 abrasive particles were mixed together; but were
distinguishable from each other visually based on color, and under
SEM based on composition) were incorporated into the pellets. The
polished cross-sections were examined using the SEM in the
secondary electron mode. The microstructure observed after heating
was substantially the same as the microstructure observed before
heating. The color of the Example 11 abrasive particles after
heating with the vitrified bonding material was the same as before
heating (i.e., white-blue).
Example 12
[0222] A lanthanum carbonate powder (obtained from Aptech Services,
LLC, Houston, Tex.; Lot No.: SH99-5-7) was heated to 900.degree. C.
to convert it to lanthanum oxide and some cerium (IV) oxide
(manufacturer's conversion specifications were 95% La.sub.2O.sub.3
and 4.19% CeO.sub.2, with a carbonate to oxide yield of 49.85 wt.%
metal oxide). Example 12 fused material, abrasive particles, and
discs were prepared as described in Example 1, except (a) the
polyethylene bottle was charged with 148.6 grams of the
lanthanum/cerium oxide powder, 146.4 grams of alumina powder
("APA-0.5"), 0.6 gram of a dispersing agent ("DURA D-30005") and
141.3 grams of distilled water, and (b) the powders were present in
amounts to provide 75 mole % Al.sub.2O.sub.3 and 25 mole %
La.sub.2O.sub.3/Ce.sub.2O- .sub.3. It was observed that the slurry
was significantly more viscous as compared to the slurry of Example
10. The fused material was bright orange in color.
[0223] FIG. 27 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 12 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-25 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 12 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline LaAlO.sub.3, and the dark portions
crystalline LaAl.sub.11O.sub.18. The widths of these phases
observed in the polished section were up to about 0.5 micrometer.
Further, large primary crystals (believed to be LaAlO.sub.3),
present in the form of dendrites, were observed in some areas of
the polished cross-section, indicating possible deviation of the
composition from an exact eutectic composition toward a
La.sub.2O.sub.3 rich composition.
[0224] The average microhardness of Example 12 abrasive particles
was determined, as described above in Example 1, except Example 10,
11, and 12 abrasive particles (i.e., Example 10, 11, and 12
particles were mixed together; but were distinguishable from each
other visually based on color, and under SEM based on composition)
were incorporated into the pellet. The average microhardness of
Example 12 abrasive particles was 14.8 GPa.
[0225] Several Example 12 abrasive particles (together with Example
10 and 12 abrasive particles) were heated placed in a platinum
crucible and heated to 1000.degree. C. at 50.degree. C./hour, held
at 1000.degree. C. for 4 hours (in air), and then cooled to room
temperature at about 100.degree. C./hour. The color of the Example
12 abrasive particles after heating was the same as before heating
(i.e., bright orange). The average microhardness of the Example 12
abrasive particles after heating was 14.7 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed for the Example 12 abrasive particles after
heating was substantially the same as the microstructure observed
before heating.
[0226] Several Example 12 abrasive particles (together with Example
10 and 11 abrasive particles) were also heated placed in a platinum
crucible and heated to 1000.degree. C. at 50.degree. C./hour, held
at 1000.degree. C. for 8 hours (in air), and then cooled to room
temperature at about 100.degree. C./hour. The color of the Example
12 abrasive particles after heating was the same as before heating
(i.e., bright orange). The average microhardness of the Example 12
abrasive particles after heating was 14.1 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed for the Example 12 abrasive particles after
heating was substantially the same as the microstructure observed
before heating.
[0227] The effect of two vitrified bonding materials on Example 12
abrasive particles were evaluated as described in Comparative
Example B, except Example 10, 11, and 12 particles (i.e., Example
10, 11, and 12 abrasive particles were mixed together; but were
distinguishable from each other visually based on color, and under
SEM based on composition) were incorporated into the pellets. The
polished cross-sections were examined using the SEM in the
secondary electron mode. The microstructure observed after heating
was substantially the same as the microstructure observed before
heating. The average microhardness of the Example 12 abrasive
particles after heating in the two vitrified bonding materials was
14.2 GPa and 14.3 GPa, respectively. The color of the Example 12
abrasive particles after heating with each of the two vitrified
bonding materials was the same as before heating (i.e., bright
orange).
Grinding Performance of Examples 9-12 and Comparative Examples
A-C
[0228] The grinding performance of Examples 9-12 and Comparative
Examples A-C coated abrasive discs were evaluated as described for
Example 1 and Comparative Examples A-C. The results are reported in
Table 4, below.
4TABLE 4 Example Total cut, g Final cut, g Comp. A 418 23 Comp. B
621 48 Comp. C 859 75 9 732 56 10 585 41 11 603 37 12 564 34
Example 13
[0229] Example 13 fused material and abrasive particles were
prepared as described in Example 1, except (a) the polyethylene
bottle was charged with 144.5 grams of alumina powder ("APA-0.5"),
147.4 grams of cerium (IV) oxide (CeO.sub.2) powder, (obtained from
Aldrich Chemical Company, Inc., Milwaukee, Wis.), 0.6 gram of a
dispersing agent ("DURAMAX D-30005"), and 137.5 grams of distilled
water, (b) the powders were present in amounts to provide 75 mole %
Al.sub.2O.sub.3 and 25 mole % Ce.sub.2O.sub.3. The fused material
was intense yellow-green in color.
[0230] FIG. 28 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 13 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-30 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 13 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline CeAlO.sub.3 and crystalline
CeO.sub.2, and the dark portions crystalline CeAl.sub.11O.sub.18.
The widths of these phases observed in the polished section were up
to about 0.5 micrometer. Further, large primary crystals (believed
to be CeAlO.sub.3 and/or CeO.sub.2), present in the form of
dendrites, were observed in some areas of the polished
cross-section, indicating possible deviation of the composition
from an exact eutectic composition toward a CeAlO.sub.3 and/or
CeO.sub.2 rich composition.
Example 14
[0231] Example 14 fused material and abrasive particles were
prepared as described in Example 1, except (a) the polyethylene
bottle was charged with 146.5 grams of alumina powder ("APA-0.5"),
147.4 grams of dysprosium oxide powder (obtained from Aldrich
Chemical Company, Inc., Milwaukee, Wis.), 0.6 gram of a dispersing
agent ("DURAMAX D-30005"), and 136.3 grams of distilled water, and
(b) the powders were present in amounts to provide 78 mole %
Al.sub.2O.sub.3 and 22 mole % Dy.sub.2O.sub.3. The fused material
was white in color.
[0232] FIG. 29 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 14 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-20 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 14 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline Dy.sub.3Al.sub.5O.sub.12, and the
dark portions .alpha.-Al.sub.2O.sub.3. The widths of these phases
observed in the polished section were up to about 1 micrometer.
Primary crystals were not observed.
Example 15
[0233] Example 15 fused material and abrasive particles were
prepared as described in Example 1, except (a) the polyethylene
bottle was charged with 146.3 grams of alumina powder ("APA-0.5"),
148.4 grams of ytterbium oxide powder (obtained from Aldrich
Chemical Company, Inc.), 0.6 gram of a dispersing agent ("DURAMAX
D-30005"), and 139.6 grams of distilled water, (b) the powders were
present in amounts to provide 78.6 mole % Al.sub.2O.sub.3 and 21.4
mole % Yb.sub.2O.sub.3. The fused material was gray in color.
[0234] FIG. 30 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 15 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies are about 5-25 micrometers in size. Based on
powder x-ray diffraction of a portion of Example 15 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline Yb.sub.3Al5O.sub.12, and the dark portions
.alpha.-Al.sub.2O.sub.3. The width of these phases observed in the
polished section were up to about 1 micrometer. Further, large
primary crystals (believed to be .alpha.-Al.sub.2O.sub.3), present
in the form of dendrites, were observed in some areas of the
polished cross-section, indicating possible deviation of the
composition from an exact eutectic composition toward an
Al.sub.2O.sub.3 rich composition.
Example 16
[0235] Example 16 fused material and abrasive particles were
prepared as described in Example 1, except the polyethylene bottle
was charged with 122.4 grams of alumina powder ("APA-0.5"), 132.6
grams of ytterbium oxide powder (obtained from Aldrich Chemical
Company, Inc), 45 grams of zirconium oxide powder (with a nominal
composition of 100 wt % ZrO.sub.2 (+HfO.sub.2); obtained under the
trade designation "DK-2" from Zirconia Sales, Inc. of Marietta,
Ga.), 0.6 gram of a dispersing agent ("DURAMAX D-30005"), and 140.2
grams of distilled water. The fused material was white-gray in
color.
[0236] FIG. 32 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 16 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-25 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 16 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline Yb.sub.3Al.sub.5O.sub.12, and the
dark portions crystalline .alpha.-Al.sub.2O.sub.3. The shape of
ZrO.sub.2 crystallites was not easily discerned on the
photomicrograph. The widths of these phases observed in the
polished section were up to about 1 micrometer.
Example 17
[0237] Example 17 fused material, abrasive particles, and discs
were prepared as described in Example 1, except a polyethylene
bottle was charged with 127.25 grams of alumina powder ("APA-0.5"),
127.75 grams of gadolinium oxide powder (obtained from Molycorp,
Inc.), 45 grams of zirconium oxide powder ("DK-2"), 0.6 gram of a
dispersing agent ("DURAMAX D-30005"), and 150 grams of distilled
water.
[0238] FIG. 33 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 17 material. The photomicrograph shows
a eutectic-derived microstructure. Based on powder x-ray
diffraction of a portion of Example 17 material, and examination of
the polished sample using SEM in the backscattered mode, it is
believed that the white portions in the photomicrograph were
crystalline GdAlO.sub.3, and the dark portions
.alpha.-Al.sub.2O.sub.3. The shape of ZrO.sub.2 crystallites was
not easily discerned on the photomicrograph. The width of the
crystals of phases observed in the polished section were up to
about 1 micrometer.
Example 18
[0239] Example 18 fused material and abrasive particles were
prepared as described in Example 1 except the polyethylene bottle
was charged with 124.5 grams of alumina powder ("APA-0.5"), 125.3
grams of dysprosium oxide powder (obtained from Aldrich Chemical
Company, Inc.), 45 grams of zirconium oxide powder ("DK-2"), 0.6
gram of a dispersing agent ("DURAMAX D-30005"), and 140 grams of
distilled water.
[0240] FIG. 34 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 18 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-15 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 18 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline Dy.sub.3Al.sub.5O.sub.12, and the
dark portions .alpha.-Al.sub.2O.sub.3. The shape of ZrO.sub.2
crystallites was not easily discerned on the photomicrograph. The
width of the crystals of phases observed in the polished section
were up to about 1 micrometer.
[0241] The average microhardness of Example 18 abrasive particles
was determined, as described above in Example 1, to be 14.8
GPa.
[0242] Several Example 18 abrasive particles were placed in a
platinum crucible and heated to 1000.degree. C. at 50.degree.
C./hour, held at 1000.degree. C. for 8 hours (in air), and then
cooled to room temperature at about 100.degree. C./hour. The
average microhardness of the Example 18 abrasive particles after
heating was 15.6 GPa. The polished cross-sections prepared for the
microhardness measurements were examined using the SEM in the
secondary electron mode. The microstructure observed for the
Example 18 abrasive particles after heating was substantially the
same as the microstructure observed before heating.
Example 19
[0243] Example 19 fused material and abrasive particles were
prepared as described in Example 1, except the polyethylene bottle
was charged with 147.9 grams of alumina powder ("APA-0.5"), 137.1
grams of lanthanum oxide powder (obtained from Molycorp, Inc.), 15
grams of zirconium oxide powder ("DK-2"), 0.6 gram of a dispersing
agent ("DURAMAX D-30005"), and 145 grams of distilled water.
[0244] FIG. 35 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 19 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-20 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 19 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline LaAlO.sub.3, the dark portions
crystalline LaAl.sub.11O.sub.18, and the gray portions crystalline,
monoclinic-ZrO.sub.2. The widths of these phases observed in the
polished section were up to about 1.5 micrometer.
Example 20
[0245] Example 20 fused material, abrasive particles, and discs
were prepared as described in Example 1, except the polyethylene
bottle was charged with 109 grams of alumina powder ("APA-0.5"),
101 grams of lanthanum oxide powder (obtained from Molycorp, Inc.),
90 grams of zirconium oxide powder ("DK-2"), 0.6 gram of a
dispersing agent ("DURAMAX D-30005"), and 145 grams of distilled
water.
[0246] FIG. 36 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 20 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. Based on powder x-ray diffraction of a portion of Example
20 material, and examination of the polished sample using SEM in
the backscattered mode, it is believed that the white portions in
the photomicrograph were crystalline LaAlO.sub.3, the dark portions
crystalline LaAl.sub.11O.sub.18, and the gray portions
La.sub.2Zr.sub.2O.sub.7. Further, based on powder x-ray
diffraction, the material also contained monoclinic and two
variants of cubic ZrO.sub.2. The shape and location of ZrO.sub.2
crystallites was not easily discerned on the photomicrograph.
[0247] The average microhardness of Example 20 abrasive particles
was determined, as described above in Example 1, to be 12.0
GPa.
[0248] Several Example 20 abrasive particles were also placed in a
platinum crucible and heated to 1000.degree. C. at 50.degree.
C./hour, held at 1000.degree. C. for 8 hours (in air), and then
cooled to room temperature at about 100.degree. C./hour. The
average microhardness of the Example 20 abrasive particles after
heating was 11.8 GPa. The polished cross-sections prepared for the
microhardness measurements were examined using the SEM in the
secondary electron mode. The microstructure observed for the
Example 20 abrasive particles after heating was substantially the
same as the microstructure observed before heating.
[0249] The grinding performance of Examples 17 and 20, and
Comparative Examples A-C coated abrasive discs were evaluated as
described above for Example 1 and Comparative Examples A-C. The
results are reported in Table 5, below.
5TABLE 5 Example Total cut, g Final cut, g Comp. A 404 21 Comp. B
647 51 Comp. C 952 79 17 669 50 20 611 41
Example 21
[0250] Example 21 fused material, abrasive particles, and discs
were prepared as described in Example 1, except the polyethylene
bottle was charged with 109 grams of alumina powder ("APA-0.5"),
101 grams of lanthanum oxide powder (obtained from Molycorp, Inc.),
9 grams of yttrium oxide powder (obtained from H. C. Starck,
Newton, Mass.), 81 grams of zirconium oxide powder ("DK-2"), 0.6
gram of a dispersing agent ("DURAMAX D-30005"), and 145 grams of
distilled water.
[0251] FIG. 37 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 21 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. Based on powder x-ray diffraction of a portion of Example
21 material, and examination of the polished sample using SEM in
the backscattered mode, it is believed that the white portions in
the photomicrograph were crystalline LaAlO.sub.3, the dark portions
crystalline LaAl.sub.11O.sub.18, and the gray portions cubic
ZrO.sub.2. The shape and location of ZrO.sub.2 crystallites was not
easily discerned on the photomicrograph.
Example 22
[0252] Example 22 fused material and abrasive particles were
prepared as described in Example 1, except the polyethylene bottle
was charged with 117 grams of alumina powder ("APA-0.5"), 93 grams
of neodymium oxide powder (obtained from Molycorp, Inc.), 90 grams
of zirconium oxide powder ("DK-2"), 0.6 gram of a dispersing agent
("DURAMAX D-30005"), and 138 grams of distilled water.
[0253] FIG. 38 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 22 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. Based on powder x-ray diffraction of a portion of Example
22 material, and examination of the polished sample using SEM in
the backscattered mode, it is believed that the white portions in
the photomicrograph were crystalline NdAlO.sub.3, and the dark
portions crystalline NdAl.sub.11O.sub.18. The widths of these
phases observed in the polished section were up to about 3
micrometers. Further, based on powder x-ray diffraction, the
material also contains two variants of cubic ZrO.sub.2. The shape
and location of ZrO.sub.2 crystallites was not easily discerned on
the photomicrograph.
Example 23
[0254] Example 23 fused material and abrasive particles were
prepared as described in Example 1, except the polyethylene bottle
was charged with 106.1 grams of alumina powder ("APA-0.5"), 103.9
grams of cerium (IV) oxide (CeO.sub.2) powder, (obtained from
Aldrich Chemical Company, Inc.), 90 grams of zirconium oxide powder
("DK-2") 0.6 gram of a dispersing agent ("DURAMAX D-30005"), and
139.5 grams of distilled water.
[0255] FIG. 39 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 23 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. Based on powder x-ray diffraction of a portion of Example
23, and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline CeAlO.sub.3, the dark portions
crystalline CeAl.sub.11O.sub.18, and the gray portions
Ce.sub.2Zr.sub.2O.sub.7. The widths of these phases observed in the
polished section were up to about 5 micrometers. Further, based on
powder x-ray diffraction, the material also contained monoclinic
and two variants of cubic ZrO.sub.2. The shape and location of
ZrO.sub.2 crystallites was not easily discerned on the
photomicrograph. Further, large primary crystals (believed to be
CeAlO.sub.3 and/or CeO.sub.2) were observed in some areas of the
polished cross-section, indicating possible deviation of the
composition from an exact eutectic composition toward a CeAlO.sub.3
and/or CeO.sub.2 rich composition.
Example 24
[0256] Example 24 fused material, abrasive particles, and discs
were prepared as described in Example 1, except (a) the
polyethylene bottle was charged with 155.6 grams of alumina powder
("APA-0.5"), 144.3 grams of lanthanum oxide powder (obtained from
Molycorp, Inc., Brea, Calif.), 0.6 gram of a dispersing agent
("DURAMAX D-30005"), and 130 grams of distilled water, and (b) the
powders were present in amounts to provide 77.5 mole %
Al.sub.2O.sub.3 and 22.5 mole % La.sub.2O.sub.3. The fused material
was white-red in color; although some of the abrasive particles
were redder than others.
[0257] FIG. 40 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 24 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-30 micrometers in size. Based
on powder x-ray diffraction of a portion of Example 24 material,
and examination of the polished sample using SEM in the
backscattered mode, it is believed that the white portions in the
photomicrograph were crystalline LaAlO.sub.3, and the dark portions
crystalline LaAl.sub.11O.sub.18. The widths of these phases
observed in the polished section were up to about 0.5 micrometer.
Further, large primary crystals (believed to be LaAlO.sub.3),
present in the form of dendrites, were observed in some areas of
the polished cross-section, indicating possible deviation of the
composition from an exact eutectic composition toward a
La.sub.2O.sub.3 rich composition.
[0258] The grinding performance of Example 24 and Comparative
Examples A-C coated abrasive discs were evaluated as described
above for Example 1 and Comparative Examples A-C. The results are
reported in Table 6, below.
6TABLE 3 Example Total cut, g Final cut, g Comp. A 404 21 Comp. B
647 51 Comp. C 952 79 24 690 52
Example 25
[0259] Example 25 fused material, abrasive particles, and discs
were prepared as described in Example 1, except the polyethylene
bottle was charged with 191.8 grams of alumina powder ("APA-0.5"),
93.2 grams of yttrium oxide powder (obtained from H. C. Starck,
Newton, Mass.), 15 grams of aluminum nitride powder (Type F;
obtained from Tokuyama Soda Co., Japan), and 150 grams of isopropyl
alcohol. The fused material was dark gray in color.
[0260] FIG. 41 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 25 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-25 micrometers in size. The
orientation and morphology of crystals making up the colonies
varied from one colony to another. Based on powder x-ray
diffraction of a portion of Example 25 material, and examination of
the polished sample using SEM in the backscattered mode, it is
believed that the white portions in the photomicrograph were
crystalline Y.sub.3Al.sub.5O.sub.12, and the dark portions
Al.sub.3O.sub.3N. The widths of these phases observed in the
polished section were up to about 1 micrometer.
[0261] The average microhardnesses of Example 25 abrasive particles
was determined, as described above in Example 1, to be 16.2
GPa.
[0262] Several Example 25 abrasive particles were heated placed in
a platinum crucible and heated to 1000.degree. C. at 50.degree.
C./hour, held at 1000.degree. C. for 4 hours (in air), and then
cooled to room temperature at about 100.degree. C./hour. The color
of the abrasive particles after heating was the same as before
heating (i.e., dark gray). The average microhardness of the
abrasive particles after heating was 16.1 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed after heating was substantially the same as
the microstructure observed before heating.
[0263] Several Example 25 abrasive particles were also heated
placed in a platinum crucible and heated to 1000.degree. C. at
50.degree. C./hour, held at 1000.degree. C. for 8 hours (in air),
and then cooled to room temperature at about 100.degree. C./hour.
The color of the abrasive particles after heating was the same as
before heating (i.e., dark gray). The average microhardness of the
abrasive particles after heating was 15.8 GPa. The polished
cross-sections prepared for the microhardness measurements were
examined using the SEM in the secondary electron mode. The
microstructure observed after heating was substantially the same as
the microstructure observed before heating.
Grinding Performance of Example 25 and Comparative Examples A-C
[0264] The grinding performance of Example 25 and Comparative
Examples A-C coated abrasive discs were evaluated as described for
Example 1 and Comparative Examples A-C. The results are reported in
Table 7, below.
7TABLE 7 Example Total cut, g Final cut, g Comp. A 414 24 Comp. B
637 50 Comp. C 988 90 25 885 69
Example 26
[0265] Example 26 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 199.9
grams of alumina powder ("APA-0.5"), 97.1 grams of yttrium oxide
powder (obtained from H. C. Starck), 3 grams of aluminum nitride
powder (Type F), and 150 grams of isopropyl alcohol.
[0266] FIG. 42 is an SEM photomicrograph of a polished section
(prepared as described in Example 1) of fused Example 26 material.
Referring to FIG. 42, the photomicrograph shows a eutectic-derived
microstructure comprising a plurality of colonies. The colonies
were about 5-30 micrometers in size. The orientation and morphology
of crystals making up the colonies varied from one colony to
another. Based on powder x-ray diffraction of a portion of Example
26 material, and examination of the polished sample using SEM in
the backscattered mode, it is believed that the white portions in
the photomicrograph were crystalline Y.sub.3Al.sub.5O.sub.12, and
the dark portions Al.sub.2O.sub.3 and Al.sub.3O.sub.3N (material
was found to contain both of these phases). The widths of these
phases observed in the polished section were up to about 3
micrometers.
Example 27
[0267] Example 27 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 171.6
grams of alumina powder ("APA-0.5"), 83.4 grams of yttrium oxide
powder (obtained from H. C. Starck), 45 grams of aluminum nitride
powder (Type F), and 150 grams of isopropyl alcohol.
[0268] FIG. 43 is an SEM photomicrograph of a polished section
(prepared as described in Example 1) of fused Example 27 material.
Referring to FIG. 43, the photomicrograph shows a eutectic-derived
microstructure comprising a plurality of colonies. The colonies
were about 5-30 micrometers in size. The orientation and morphology
of crystals making up the colonies varied from one colony to
another. FIG. 43 also shows the presence of a third phase in the
form of largely spherical inclusions. Based on powder x-ray
diffraction of a portion of Example 27 material, and examination of
the polished sample using SEM in the backscattered mode, it is
believed that the white portions in the photomicrograph were
crystalline Y.sub.3Al.sub.5O.sub.12, and the dark portions
Al.sub.3O.sub.3N. The dark inclusions are believed to be AIN phase.
The widths of crystals of Y.sub.3Al.sub.5O.sub.12 and
Al.sub.3O.sub.3N phases observed in the polished section were up to
about 3 micrometers.
Example 28
[0269] Example 28 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 181.7
grams of alumina powder ("APA-0.5"), 88.3 grams of yttrium oxide
powder (obtained from Alfa Aesar A Johnson Matthey Company, Ward
Hill, Mass.), 30 grams of aluminum carbide powder (obtained from
Aldrich Chemical Co., Milwaukee, Wis.),, and 150 grams of isopropyl
alcohol.
[0270] FIG. 44 is an SEM photomicrograph of a polished section
(prepared as described in Example 1) of fused Example 28 material.
Referring to FIG. 44, the photomicrograph shows a eutectic-derived
microstructure comprising a plurality of colonies. The colonies
were about 5-30 micrometers in size. The orientation and morphology
of crystals making up the colonies varied from one colony to
another. Based on powder x-ray diffraction of a portion of Example
28 material, and examination of the polished sample using SEM in
the backscattered mode, it is believed that the white portions in
the photomicrograph were crystalline Y.sub.3Al.sub.5O.sub.12, and
the dark portions Al.sub.2OC. The widths of these phases observed
in the polished section were up to about 3 micrometers.
Example 29
[0271] Example 29 fused abrasive particles and coated abrasive
discs were prepared as described in Example 1, except the
polyethylene bottle was charged with 135.3 grams of alumina powder
("APA-0.5"), 143.7 grams of gadolinium oxide powder (obtained from
Molycorp, Inc., Brea, Calif.), 21 grams of aluminum nitride powder
(Type F), and 150 grams of isopropyl alcohol. The fused material
was dark gray in color.
[0272] FIG. 45 is a scanning electron microscope (SEM)
photomicrograph of a polished section (prepared as described in
Example 1) of fused Example 29 material. The photomicrograph shows
a eutectic-derived microstructure comprising a plurality of
colonies. The colonies were about 5-25 micrometers in size. The
orientation and morphology of crystals making up the colonies
varied from one colony to another. Based on powder x-ray
diffraction of a portion of Example 29 material, and examination of
the polished sample using SEM in the backscattered mode, it is
believed that the white portions in the photomicrograph were
crystalline GdAlO.sub.3, and the dark portions Al.sub.3O.sub.3N. In
addition, the presence of Al.sub.2O.sub.3 was also detected by
powder x-ray diffraction. The widths of the GdAlO.sub.3 and
Al.sub.3O.sub.3N phases observed in the polished section were up to
about 1 micrometer.
[0273] The average microhardnesses of Example 29 abrasive particles
was determined, as described above in Example 1, to be 17.2
GPa.
[0274] Several Example 29 abrasive particles were heated placed in
a platinum crucible and heated to 1000.degree. C. at 50.degree.
C./hour, held at 1000.degree. C. for 8 hours (in air), and then
cooled to room temperature at about 100.degree. C./hour. The color
of the abrasive particles after heating was the same as before
heating. The average microhardness of the abrasive particles after
heating was 17.1 GPa. The polished cross-sections prepared for the
microhardness measurements were examined using the SEM in the
secondary electron mode. The microstructure observed after heating
was substantially the same as the microstructure observed before
heating.
Grinding Performance of Example 29 and Comparative Examples A-C
[0275] The grinding performance of Example 29 and Comparative
Examples A-C coated abrasive discs were evaluated as described for
Example 1 and Comparative Examples A-C. The results are reported in
Table 8, below
8TABLE 8 Example Total cut, g Final cut, g Comp. A 414 24 Comp. B
637 50 Comp. C 988 90 29 825 50
Example 30
[0276] Example 30 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 138.5
grams of alumina powder ("APA-0.5"), 140.5 grams of ytterbium oxide
powder (obtained from Aldrich Chemical Company, Inc.), 21 grams of
aluminum nitride powder (Type F), and 150 grams of isopropyl
alcohol.
[0277] FIG. 46 is an SEM photomicrograph of a polished section
(prepared as described in Example 1) of fused Example 30 material.
The photomicrograph shows a eutectic-derived microstructure
comprising a plurality of colonies. The colonies were about 5-30
micrometers in size. The orientation and morphology of crystals
making up the colonies varied from one colony to another. Based on
powder x-ray diffraction of a portion of Example 30 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline Yb.sub.3Al.sub.5O.sub.12- , and the dark portions
Al.sub.2O.sub.3 and Al.sub.3O.sub.3N (material was found to contain
both of these phases). The widths of these phases observed in the
polished section were up to about 2 micrometers.
Example 31
[0278] Example 31 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 139
grams of alumina powder ("APA-0.5"), 140 grams of dysprosium oxide
powder (obtained from Aldrich Chemical Company Inc.), 21 grams of
aluminum nitride powder (Type F), and 150 grams of isopropyl
alcohol.
[0279] FIG. 47 is an SEM photomicrograph of a polished section
(prepared as described in Example 1) of fused Example 31 material.
The photomicrograph shows a eutectic-derived microstructure
comprising a plurality of colonies. The colonies were about 5-30
micrometers in size. The orientation and morphology of crystals
making up the colonies varied from one colony to another. Based on
powder x-ray diffraction of a portion of Example 31 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline Dy.sub.3Al.sub.5O.sub.12- , and the dark portions
Al.sub.3O.sub.3N. The widths of crystals of
Dy.sub.3Al.sub.5O.sub.12 and Al.sub.3O.sub.3N phases observed in
the polished section were up to about 2 micrometers.
Example 32
[0280] Example 32 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 135.3
grams of alumina powder ("APA-0.5"), 143.7 grams of gadolinim oxide
powder (obtained from Molycorp, Inc., Brea, Calif.), 21 grams of
aluminum carbide powder (obtained from Aldrich Chemical Co.), and
150 grams of isopropyl alcohol.
[0281] FIG. 48 is an SEM photomicrograph of a polished section
(prepared as described in Example 1) of fused Example 32 material.
The photomicrograph shows a eutectic-derived microstructure
comprising a plurality of colonies. The colonies were about 5-30
micrometers in size. The orientation and morphology of crystals
making up the colonies varied from one colony to another. Based on
powder x-ray diffraction of a portion of Example 32 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline GdAlO.sub.3, and the dark portions Al.sub.2OC and
Al.sub.2O.sub.3 (both phases were present according to powder x-ray
diffraction.). The widths of these phases observed in the polished
section were up to about 3 micrometers.
Example 33
[0282] Example 33 fused material was prepared as described in
Example 1, except the polyethylene bottle was charged with 132.3
grams of alumina powder ("APA-0.5"), 122.7 grains of lanthanum
oxide powder (obtained from Molycorp. Inc., Brea Calif.), 45 grams
of aluminum nitride powder (Type F) and 150 grams of isopropyl
alcohol.
[0283] FIG. 49 is an SEM photomicrograph of a polished section
(prepared as described in Example 1) of fused Example 33 material.
The photomicrograph shows a eutectic-derived microstructure
comprising a plurality of colonies. The colonies were about 5-30
micrometers in size. The orientation and morphology of crystals
making up the colonies varied from one colony to another. Based on
powder x-ray diffraction of a portion of Example 33 material, and
examination of the polished sample using SEM in the backscattered
mode, it is believed that the white portions in the photomicrograph
were crystalline LaAlO.sub.3 and the dark portions
LaAl.sub.11O.sub.18. FIG. 49 also shows the presence of a third
phase in the form of largely spherical inclusions. These inclusions
are believed to be AIN phase. The widths of crystals of LaAlO.sub.3
and LaAl.sub.11O.sub.18 phases observed in the polished section
were up to about 1 micrometer.
[0284] Various modifications and alterations of this invention will
become apparent to those skilled in the art without departing from
the scope and spirit of this invention, and it should be understood
that this invention is not to be unduly limited to the illustrative
embodiments set forth herein.
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