U.S. patent application number 10/559907 was filed with the patent office on 2007-06-21 for thermally stable calcium-aluminum bulk amorphous metals with low mass density.
Invention is credited to Faqiang Guo, S. Joseph Poon, Gary J. Shiflet.
Application Number | 20070137737 10/559907 |
Document ID | / |
Family ID | 33556396 |
Filed Date | 2007-06-21 |
United States Patent
Application |
20070137737 |
Kind Code |
A1 |
Guo; Faqiang ; et
al. |
June 21, 2007 |
Thermally stable calcium-aluminum bulk amorphous metals with low
mass density
Abstract
The present invention relates to novel calcium based amorphous
alloys with high thermal stability and low mass density represented
by the general formula: CaAlQ, wherein Q represents one or more
elements selected from the group consisting of Cu, Ag, Zn and Mg.
Typically, the atomic percentage of the calcium is about 50%.
Inventors: |
Guo; Faqiang;
(Charlottesville, VA) ; Poon; S. Joseph;
(Charlottesville, VA) ; Shiflet; Gary J.;
(Charlottesville, VA) |
Correspondence
Address: |
UNIVERSITY OF VIRGINIA PATENT FOUNDATION
250 WEST MAIN STREET, SUITE 300
CHARLOTTESVILLE
VA
22902
US
|
Family ID: |
33556396 |
Appl. No.: |
10/559907 |
Filed: |
May 27, 2004 |
PCT Filed: |
May 27, 2004 |
PCT NO: |
PCT/US04/16757 |
371 Date: |
December 8, 2005 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
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60477605 |
Jun 11, 2003 |
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60490806 |
Jul 29, 2003 |
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60524506 |
Nov 24, 2003 |
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Current U.S.
Class: |
148/403 ;
420/415 |
Current CPC
Class: |
C22C 24/00 20130101;
C22C 45/00 20130101 |
Class at
Publication: |
148/403 ;
420/415 |
International
Class: |
C22C 45/00 20060101
C22C045/00 |
Goverment Interests
US GOVERNMENT RIGHTS
[0002] This invention was made with United States Government
support under an Air Force Office of Scientific Research Contract
No. F33615-01-2-5217 awarded by the Defense Advance Research
Projects Agency. The United States Government has certain rights in
the invention.
Claims
1. An amorphous alloy represented by the formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.pNi.sub.r
wherein x, y, n, m, p and r are atomic percentages, wherein x is a
number selected from about 5 to about 35; y is a number selected
from 0 to about 15; n, m, p and r are independently a number
selected from 0 to about 20, wherein y+n+m+p+r is less than 30; and
t is the sum of x, y, n, m, p and r, with the proviso that t is a
number selected from about 25 to about 55.
2. The alloy of claim 1, wherein r is 0.
3. The alloy of claim 1, wherein said alloy is processable into
bulk amorphous samples of at least about 2 mm in thickness in its
minimum dimension.
4. The alloy of claim 1, wherein said alloy has a Tg of at least
200.degree. C.
5. The alloy of claim 2, wherein x is a number selected from about
25 to about 40, and y+n+m+p is less than 20.
6. The alloy of claim 5 wherein the alloy is represented by the
formula: Ca.sub.(100-t)Al.sub.xQ.sub.g wherein Q is an element
selected from the group consisting of Cu, Ag, Zn and Mg; x is a
number selected from about 25 to about 35; g is a number selected
from 0 to about 15; and t is the sum of x and g.
7. The alloy of claim 6 wherein g is 0.
8. The alloy of claim 1 wherein the alloy is represented by the
formula: Ca.sub.tAl.sub.xQ.sub.yZn.sub.mMg.sub.p wherein Q is Cu or
Ni; t, x, y, m and p are atomic percentages, wherein t is a number
selected from about 50 to about 60; x is a number selected from
about 5 to about 15; y is a number selected from about 0 to about
10; m is a number selected from about 10 to about 20; and p is a
number selected from 10 to about 15.
9. The alloy of claim 8 wherein t is a number selected from about
55 to about 60, and p is about 15.
10. An article of manufacture comprising a calcium-based amorphous
alloy represented by the formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.pNi.sub.r
wherein x, y, n, m, p and r are atomic percentages, wherein x is a
number selected from about 5 to about 35; p is a number selected
from about 5 to about 15; r is a number selected from 0 to about
10; y, n and m are independently a number selected from 0 to about
20, wherein y+n+m is less than about 21; and t is the sum of x, y,
n, m, p and r, with the proviso that t is a number selected from
about 35 to about 55.
11. The article of manufacture of claim 10 wherein x is a number
selected from about 5 to about 15; y is a number selected from 0 to
about 15; n is 0; m is a number selected from about 10 to about 20;
p is a number selected from about 10 to about 15; r is a number
selected from 0 to about 10, and t is a number selected from about
35 to about 50.
12. The article of manufacture of claim 11 wherein the
calcium-based amorphous alloy is represented by the formula:
Ca.sub.tAl.sub.xQ.sub.yZn.sub.mMg.sub.p wherein Q is Cu or Ni; t,
x, y, m and p are atomic percentages, wherein t is a number
selected from about 50 to about 60; x is a number selected from
about 10 to about 15; y is a number selected from about 0 to about
10; m is a number selected from about 10 to about 20; and p is a
number selected from 10 to about 15.
13. The article of manufacture of claim 10 wherein the
calcium-based amorphous alloy is represented by the formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.p wherein x,
y, n, m and p are atomic percentages, wherein x is a number
selected from about 25 to about 35; n is a number selected from
about 0 to about 20; m and y are independently a number selected
from 0 to about 15, p is a number selected from about 0 to about
20; and t is the sum of x, y, n, m and p, with the proviso that t
is a number selected from about 35 to about 50.
14. A method of preparing homogeneous ingots of a CaAl-based
amorphous alloy comprising Cu or Ag, said method comprising the
steps of placing all the elements of the alloy, except the Cu and
Ag elements in a boron-nitride-coated graphite crucible; placing
the Cu and Ag elements in the crucible on top of, and in contact
with, the other alloy elements; and melting the combination
together to form a homogenous ingot.
Description
RELATED APPLICATIONS
[0001] This application claims priority under 35 USC .sctn. 119(e)
to U.S. Provisional Application Ser. Nos. 60/477,605, filed Jun.
11, 2003, 60/490,806, filed Jul. 29, 2003 and 60/524,506, filed
Nov. 24, 2003, the disclosures of which are incorporated herein by
reference.
BACKGROUND
[0003] Bulk-solidifying amorphous metal alloys (a.k.a. bulk
metallic glasses) are those alloys that can form an amorphous phase
upon cooling the melt at a rate of several hundred degrees Kelvin
per second or lower. Amorphous alloys usually exhibit certain
superior properties than their crystalline counterparts with the
same or similar compositions, such as tensile or compressive
strength, wear resistance and corrosion resistance as well as
oxidation resistance. As promising structural materials, the study
of light-metal-based amorphous alloys has grown in the past two
decades. To date, light-metal-based amorphous alloys have been
successfully prepared in several alloy systems, including Mg-TM-RE
(wherein TM represents late transition metals, such as Cu and Ni,
and RE represents rare earth metals, such as Y and La), Al-TM-RE
(including Ni, Co and Fe as the TM element and Gd and Y as the RE
element), Al--Cu--Mg--Ni and recently reported Ca--Cu--Mg
alloys.
[0004] Table 1 lists the glass transition temperature Tg, onset
temperature of crystallization Tx, reduced glass transition
temperature Trg (defined as glass transition temperature over the
melting point of the alloy in Kelvin), calculated mass density
(grams per cubic centimeter) and glass formability of several
representative light-metal-based amorphous alloy compositions. The
calculated mass density was obtained by assuming no volume
contraction or expansion when alloying the component elements
together. The glass formability was characterized by the diameter
in millimeters of the cast cylinder-shaped rod with a fully
amorphous structure or by the thickness of the ribbon-shaped
samples with a fully amorphous phase for those alloys whose glass
formability is not high enough to form bulk amorphous samples.
TABLE-US-00001 TABLE 1 Summary of representative light-metal-based
amorphous alloy compositions, together with Tg, Tx, Trg, calculated
mass density and glass formability. Calculated Tg Tx Mass Glass
Composition (at. %) (.degree. C.) (.degree. C.) Trg Density
Formability Al.sub.87Ni.sub.7Gd(Y).sub.6 N/A 210 3.18-3.58 200-300
.mu.m Al.sub.85Ni.sub.7Gd(Y).sub.8 250 280 0.45 3.24-3.76 100-150
.mu.m Mg.sub.60Cu.sub.30Y.sub.10 160 210 0.60 3.40 6 mm
(Al.sub.75Cu.sub.17Mg.sub.8).sub.95Ni.sub.5 N/A 167 3.55 100 .mu.m
Ca.sub.67Mg.sub.19Cu.sub.14 114 134 0.60 1.92 2 mm
Ca.sub.57Mg.sub.19Cu.sub.24 131 167 0.64 2.24 .gtoreq.4 mm
All the alloys listed in Table 1, except
Al.sub.85Ni.sub.7Gd(Y).sub.8 alloys, which unfortunately is not a
bulk glass former, exhibit quite low thermal stability. Their Tg,
if observable, is much less than 200.degree. C., with their Tx
being at most near 200.degree. C. From the practical point of view,
the low thermal stability of the light-metal-based bulk amorphous
alloys mentioned above has limited their application as structural
materials. It is an attractive idea to develop light-metal-based
amorphous alloys which simultaneously exhibit a large glass
formability and a high thermal stability useful for structural
applications.
SUMMARY OF VARIOUS EMBODIMENTS OF THE INVENTION
[0005] The present invention is directed to a new class of bulk
amorphous alloys based on calcium and aluminum that exhibit large
glass formability and high thermal stability and thus are useful
for structural applications. With variation of the composition, the
mass density of the CaAl-based bulk amorphous alloys ranges from
1.74 to 2.50 grams/cc, which is among the lowest values reported
for amorphous metals. The thermal stability of CaAl-based amorphous
alloys, having Al content of about 25-30 atomic percent, is much
higher than those of the Ca-based Al-free amorphous alloys
(Tg=180-240.degree. C.), while exhibiting glass formability that
allows for the preparation of cast amorphous rods having a diameter
of at least 1 mm.
BRIEF DESCRIPTION OF THE DRAWINGS
[0006] FIG. 1. represents a photograph of an as-cast 9 mm diameter
amorphous rod of Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.15Cu.sub.5
alloy.
[0007] FIG. 2. illustrates an x-ray diffraction pattern from
exemplary sample pieces (each of total mass about 1 gram) obtained
by crushing a 2 mm as-cast rods of a bulk amorphous
Ca.sub.56.5Al.sub.28.5Mg.sub.10Cu.sub.5 alloy.
[0008] FIG. 3. illustrates differential scanning calorimeter (DSC)
curves representing the crystallization and melting behavior of
high Al content CaAl-based representative alloys as marked in the
figure.
[0009] FIG. 4. represents enlarged DSC curves of FIG. 3 showing the
glass transition phenomenon of the high Al content CaAl-based
representative alloys.
[0010] FIG. 5. illustrates differential scanning calorimeter (DSC)
curves representing the crystallization and melting behavior of low
Al content CaAl-based representative alloys with compositions
marked in the figure.
DETAILED DESCRIPTION OF EMBODIMENTS
[0011] Definitions
[0012] In describing and claiming the invention, the following
terminology will be used in accordance with the definitions set
forth below.
[0013] As used herein, the term "reduced glass temperature (Trg)"
is defined as the glass transition temperature (Tg) divided by the
liquidus temperature (Tl) in K.
[0014] As used herein, the term "supercooled liquid region
(.DELTA.Tx)" is defined as crystallization temperature minus the
glass transition temperature.
[0015] As used herein, the term "calcium-based alloy" refers to
alloys wherein calcium constitutes a major component of the alloy.
Typically, the calcium-based amorphous alloys of the present
invention have a Ca content of approximately 50% or greater,
however, the Ca content of the present alloys may comprise anywhere
from 35% to 75% calcium.
[0016] As used herein, the term "amorphous alloy" is intended to
include both completely amorphous alloys (i.e. where there is no
ordering of molecules/atomic packing), as well as partially
crystalline alloys containing crystallites that range from
nanometer to the micron scale in size.
EMBODIMENTS
[0017] Aluminum-based amorphous alloys have been successfully
prepared in several alloy systems, however the previous described
light metal-based bulk glass alloys suffer the disadvantage of
exhibiting low thermal stability. Applicants have discovered a new
class of bulk amorphous alloys based on calcium and aluminum that
simultaneously exhibit large glass formability and high thermal
stability and thus are useful for structural applications.
Experimentally it was found that binary Ca--Al alloys, close to the
Ca-rich eutectic composition range, are able to form bulk
cylinder-shaped amorphous rods with a diameter up to 1 mm. This is
believed to be the first report of the formation of bulk amorphous
alloys in a binary metal system. With the further introduction of
Cu, Ag, Mg and/or Zn, the glass formability of the alloys is
improved and the diameter of the cast amorphous rods varies from 3
to 9 mm, depending on the Al content of the alloys.
[0018] In one embodiment of the present invention a calcium-based
aluminum amorphous alloy comprising at least 50% calcium is
prepared using commercial grade material to create an alloy that
can be processed into cylinder samples having a diameter of 1.0
millimeter or greater. In one embodiment the calcium-based aluminum
amorphous alloys of the present invention exhibit a Tg of at least
170.degree. C. In one embodiment calcium-based amorphous alloys
comprise at least 50% calcium and 20-35% aluminum and exhibit a Tg
greater than 200.degree. C. In another embodiment a calcium-based
amorphous alloy is provided, comprising at least 50% calcium and
10-20% aluminum, that can be cast as an amorphous rod having a
continuous diameter of about 3 to about 9 mm and exhibiting a Tg
greater than 110.degree. C. In one embodiment the bulk-solidifying
Ca-based amorphous alloys of the present invention are completely
amorphous. Since the synthesis-processing methods employed by the
present invention do not involve any special materials handling
procedures, they are directly adaptable to low-cost industrial
processing technology.
[0019] In accordance with one embodiment of the present invention,
a calcium-based amorphous alloy with enhanced glass formability and
high thermal stability properties is provided wherein the alloy is
represented by the formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.pNi.sub.r I
wherein
[0020] x, y, n, m, p and r are atomic percentages, wherein [0021] x
is a number selected from about 5 to about 35; [0022] y is a number
selected from 0 to about 15; [0023] n, m, p and r are independently
a number selected from 0 to about 20, wherein y+n+m+p+r is less
than 30; and
[0024] t is the sum of x, y, n, m, p and r, with the proviso that t
is a number selected from about 25 to about 55. In accordance with
one embodiment, an alloy of the general formula I is provided
wherein x is a number selected from about 25 to about 40, r is 0,
and y+n+m+p is less than 20. In accordance with one embodiment, an
alloy of the general formula I is provided wherein x is a number
selected from about 30 to about 40 and y, n, m, r and p are each
0.
[0025] In accordance with another embodiment, a calcium-based
amorphous alloy is provided wherein the alloy is represented by the
formula: Ca.sub.(100-t)Al.sub.xQ.sub.g II
[0026] wherein Q is an element selected from the group consisting
of Cu, Ag, Zn and Mg;
[0027] x is a number selected from about 25 to about 35;
[0028] g is a number selected from 0 to about 15; and
[0029] t is the sum of x and g.
[0030] In accordance with one embodiment, a calcium-based amorphous
alloy is provided wherein the alloy is represented by the formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.p III
wherein
[0031] x, y, n, m and p are atomic percentages, wherein [0032] x is
a number selected from about 25 to about 35; [0033] p is a number
selected from about 5 to about 15; [0034] n, m and y are
independently a number selected from 0 to about 20, wherein y+n+m+p
is less than 30; and
[0035] t is the sum of x, y, n, m and p, with the proviso that t is
a number selected from about 25 to about 55.
[0036] In accordance with one embodiment, an alloy of the general
formula III is provided wherein x is a number selected from about
25 to about 35, y and m are independently a number selected from 0
to about 10, n is a number selected from 0 to about 15, p is a
number selected from 0 to about 20, and t is the sum of x, y, n, m
and p, with the proviso that t is a number selected from about 25
to about 55.
[0037] In a further embodiment a calcium-based amorphous alloy that
exhibit a Tg greater than 200.degree. C. is provided wherein the
alloy has the general structure of formula III. More particularly
in one embodiment an alloy of the general formula III is provided
wherein x is a number selected from about 27 to about 32, y and n
are independently a number selected from 0 to about 5, m is 0, p is
about 10 to about 20, and t is a number selected from about 43 to
about 47. In another embodiment an alloy of the general formula III
is provided wherein x is a number selected from about 27 to about
30, y and n are independently a number selected from 0 to about 5,
m is 0, p is about 10 to about 15, and t is a number selected from
about 43 to about 44. In another embodiment an alloy of the general
formula III is provided wherein x is a number selected from about
27 to about 30, n is a number selected from 0 to about 10, y and m
are both 0, p is about 10 to about 15, and t is a number selected
from about 43 to about 44. In another embodiment an alloy of the
general formula III is provided wherein x is a number selected from
about 27 to about 32, n, y and m are each 0, p is about 10 to about
15, and t is a number selected from about 42 to about 45.
[0038] In another embodiment a light-metal-based amorphous alloy is
provided that has superior glass formability, allowing for the
formation of amorphous rods with diameters ranging from greater
than 2 mm to about 9 mm. Such calcium-based amorphous alloys are
represented by the general formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.pNi.sub.r I
wherein
[0039] x, y, n, m, p and r are atomic percentages, wherein [0040] x
is a number selected from about 5 to about 15; [0041] p is a number
selected from about 5 to about 15; [0042] r is a number selected
from 0 to about 10; [0043] n, m and y are independently a number
selected from 0 to about 20, wherein y+n+m is less than about 21;
and
[0044] t is the sum of x, y, n, m, p and r, with the proviso that t
is a number selected from about 35 to about 55. In accordance with
one embodiment a calcium/aluminum-based amorphous alloy is provided
that has superior glass formability, wherein the alloy is
represented by formula I wherein x is a number selected from about
5 to about 15, y is a number selected from 0 to about 15, n is 0, m
is a number selected from about 10 to about 20, p is a number
selected from about 10 to about 15, r is a number selected from 0
to about 10, and t is a number selected from about 35 to about
50.
[0045] In accordance with one embodiment, a calcium-based amorphous
alloy is provided wherein the alloy is represented by the formula:
Ca.sub.tAl.sub.xQ.sub.yZn.sub.mMg.sub.p IV wherein Q is Cu or
Ni;
[0046] t, x, y, m and p are atomic percentages, wherein [0047] t is
a number selected from about 50 to about 60; [0048] x is a number
selected from about 10 to about 15; [0049] y is a number selected
from about 5 to about 10; [0050] m is a number selected from about
10 to about 20; and [0051] p is a number selected from 10 to about
15. In accordance with one embodiment a calcium/aluminum-based
amorphous alloy is provided that has superior glass formability,
wherein the alloy is represented by formula IV wherein t is a
number selected from about 55 to about 60, x is about 10, y is a
number selected from 0 to about 10, m is a number selected from
about 10 to about 20 and p is a number selected from about 10 to
about 15.
[0052] The CaAl-based bulk amorphous alloys of the present
invention can be formulated to generate higher thermal stability or
higher glass formability properties by manipulating the aluminum
content of the alloy. More particularly, "high Al" content alloys,
containing 25-35 atomic percent Al, exhibit a thermal stability
much higher than those of the Ca-based Al-free amorphous alloys.
Typically, the high Al amorphous alloys exhibit a Tg of greater
than 200.degree. C. and a Tx ranging from about 220 to about
270.degree. C. "Low Al" content alloys, containing 5-15 atomic
percent Al, are able to form amorphous rods having a diameter of at
least 3 mm and up to about 9 mm. These low Al content Ca--Al
amorphous alloys exhibit a Tg ranging from 120 to 150.degree. C.
and Tx from 150 to more than 200.degree. C., and thus they exhibit
greater glass formability at the sacrifice of some of the thermal
stability. However, these low Al amorphous alloys are better suited
in GFA than previously described Ca-alloys.
[0053] With variation of the composition, the mass density of the
CaAl-based bulk amorphous alloys ranges from 1.74 to 2.50 grams/cc,
which is among the lowest values reported for amorphous metals.
Preliminary measurement of the CaAl-based amorphous alloys shows
that the microhardness is in the range of 200-240/DPH. According to
the empirical relationship between the microhardness value and the
mechanical strength, these amorphous alloys are expected to exhibit
a fracture tensile strength around 700-800 MPa This value is about
40% higher than that of the previously disclosed Ca-based Al-free
amorphous alloys, where a compressive fracture strength of 545 MPa
was reported for the alloy Ca.sub.57Mg.sub.19Cu.sub.24. The good
combination of large glass formability, low mass density, high
thermal stability and mechanical properties indicates that the
CaAl-based amorphous alloys could be a promising structural
material where comprehensive properties are required.
[0054] The present alloys may be devitrified to form
amorphous-crystalline microstructures, or infiltrated with other
ductile phases during solidification or melting of the amorphous
alloys in the supercooled-liquid region, to form composite
materials, which can result in strong hard products with improved
ductility for structural applications. In accordance with one
embodiment of the invention, the alloys can be made to exhibit the
formation of quasi-crystals upon cooling at a rate somewhat slower
than the critical cooling rate for glass formation. In this case,
the alloy can solidify into a composite structure consisting of
quasi-crystalline precipitates embedded in an amorphous matrix. In
this way, high strength bulk quasi-crystalline materials can be
produced and thus the range of practical applications is extended.
For example, quasi-crystalline materials typically have very low
coefficients of friction and high hardness, making them useful for
bearing applications.
[0055] In accordance with one embodiment of the present invention,
an article of manufacture is provided wherein the article comprises
a light-metal-based amorphous alloy represented by the formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.pNi.sub.r I
wherein
[0056] x, y, n, m, p and r are atomic percentages, wherein [0057] x
is a number selected from about 5 to about 15; [0058] p is a number
selected from about 5 to about 15; [0059] r is a number selected
from 0 to about 10; [0060] n, m and y are independently a number
selected from 0 to about 20, wherein y+n+m is less than about 21;
and
[0061] t is the sum of x, y, n, m, p and r, with the proviso that t
is a number selected from about 35 to about 55. In accordance with
one embodiment a calcium/aluminum-based amorphous alloy is provided
that has superior glass formability, wherein the alloy is
represented by formula I wherein x is a number selected from about
5 to about 15, y is a number selected from 0 to about 15, n is 0, m
is a number selected from about 10 to about 20, p is a number
selected from about 10 to about 15, r is a number selected from 0
to about 10, and t is a number selected from about 35 to about
50.
[0062] In accordance with another embodiment, an article of
manufacture is provided wherein the article comprises a
calcium-based amorphous alloy represented by the formula:
Ca.sub.tAl.sub.xQ.sub.yZn.sub.mMg.sub.p IV wherein Q is Cu or
Ni;
[0063] t, x, y, m and p are atomic percentages, wherein [0064] t is
a number selected from about 50 to about 60; [0065] x is a number
selected from about 10 to about 15; [0066] y is a number selected
from about 0 to about 10; [0067] m is a number selected from about
10 to about 20; and [0068] p is a number selected from 10 to about
15.
[0069] In accordance with another embodiment, an article of
manufacture is provided wherein the article comprises a CaAl-based
amorphous alloy represented by the formula:
Ca.sub.(100-t)Al.sub.xCu.sub.yAg.sub.nZn.sub.mMg.sub.p wherein
[0070] x, y, n, m and p are atomic percentages, wherein [0071] x is
a number selected from about 25 to about 35; [0072] n is a number
selected from about 0 to about 20; [0073] m and y are independently
a number selected from 0 to about 15, [0074] p is a number selected
from about 0 to about 20; and
[0075] t is the sum of x, y, n, m and p, with the proviso that t is
a number selected from about 30 to about 50.
[0076] Owing to the good glass formability, CaAl-based alloys can
be produced into various forms of amorphous alloys, such as thin
ribbon samples by melt spinning, amorphous powders by atomization,
amorphous rods, sheets and/or plates by casting. The casting can be
carried out using conventional injection casting, die casting,
squeeze casting, suction casting and strip casting as well as other
state-of the-art casting techniques currently employed in research
labs and industries. Owing to the existence of a distinct
supercooled liquid region, it is very promising to utilize the
formability of the CaAl-based amorphous alloys in the supercooled
liquid region to form desired shapes of frames and parts without
further machining.
[0077] The combination of low mass density, high thermal stability
and mechanical properties as well as good glass formability make
the present CaAl-based amorphous alloys promising structural
materials having applications where high comprehensive properties
are required. The alloys can be used in a variety of applications
including use as coatings to provide oxidation and/or corrosion
resistant layers and use as structural materials under extreme
environments. Ceramic particles or fibers and/or refractory metal
particles can be blended with atomized CaAl-based alloy powders,
and by extrusion, used to produce composite materials for
structural applications. Alternatively, the present alloys may be
devitrified partially to form amorphous-crystalline composite
materials.
[0078] The present CaAl-based amorphous alloys may be used in many
application areas. Some of the products and services to which the
present invention can be implemented include, but are not limited
thereto 1) vehicle (land-craft and aircraft) frames and parts, 2)
engineering, construction, and medical materials and tools and
devices, 3) laminate composite: laminate with other structural
alloys (e.g. Mg, Al, Fe, and Ti to name a few) for aerospace
applications, 4) other utilizations that require the combination of
specific properties realizable by the present Ca-based amorphous
alloys. CaAl-based metallic glasses may also have other useful
functional applications in addition to their mechanical properties.
As important as its potential practical application, from the
scientific point of view, CaAl-based amorphous alloys (especially
the binary Ca--Al alloy), provide an ideal system to study the
fundamental issues related to glass formability of alloy
systems.
EXAMPLE 1
Preparation of CaAl-Based Amorphous Alloys
Ingot Preparation
[0079] Alloy ingots were prepared by melting mixtures of high
purity elements in an induction furnace. Boron-nitride-coated
graphite crucibles are used as the melting boat in the preparation
of alloy ingots. For the Cu and Ag-containing alloys, Cu and Ag
elements are placed on the top of the raw materials. Because Cu and
Ag are materials with the highest melting points in these alloy
system, they will be the last ones to be melted during melting.
Arranging the elements in this way allows direct observation of the
melting of Cu and/or Ag, which then react with the melted material,
assuring a homogeneous composition.
Glass Formability
[0080] The amorphous samples were produced preliminarily via
conventional copper mold casting, which is realized by injecting
the alloy melt into a cylinder-shaped cavity inside a water-cooled
copper block. Thermal transformation data were acquired using a
Differential Scanning calorimeter (DSC). The designed CaAl-based
amorphous alloys exhibit a reduced glass transition temperature Trg
in the range 0.56-0.63 and a supercooled liquid region .DELTA.T in
the range 20-50.degree. C. The alloys of this invention can be cast
into amorphous rods with diameters reaching up to 3-9 mm, depending
on the Al content employed. A picture of the 9 mm as-cast amorphous
rod of Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.15Cu.sub.5 alloy is shown
in FIG. 1. The amorphous nature of the cast rods is verified by
x-ray diffraction and DSC measurement (see FIGS. 2 through 5).
EXAMPLE 2
High Al Content (25-35 at. %) Ca--Al-Based Alloys
[0081] With Al as the main additive, the strong interaction of Al
with Ca and the unique network microstructure between Ca and Al
atoms give the high thermal stability of the designed amorphous
alloys. Introducing additional elements such as Mg, Cu, Ag, Zn,
further improves the glass formability of the alloys, resulting in
binary (CaAl), ternary (CaAlCu, CaAlAg, CaAlMg, CaAlZn), quaternary
(CaAlCuAg, CaAlMgCu, CaAlMgAg, CaAlMgZn and CaAlCu(Ag)Zn) and
quinary (CaAlMgCuAg, CaAlMgCuZn and CaAlMgAgZn) alloys. Exemplary
alloys include those represented by the following formulas (in
atomic percent)
Binary Alloys
[0082] Ca.sub.100-xAl.sub.x
[0083] where 32.ltoreq.x.ltoreq.37
Ternary Alloys
[0084] Ca.sub.100-x-yAl.sub.xCu(Ag,Mg,Zn).sub.y
[0085] where 27.ltoreq.x.ltoreq.35, 0.ltoreq.y.ltoreq.20
Quaternary Alloys
[0086] Ca.sub.100-x-yAl.sub.x(A.sub.aB.sub.b).sub.y
[0087] where 27.ltoreq.x.ltoreq.35, 0.ltoreq.y.ltoreq.17,
0.ltoreq.a,b.ltoreq.100, and AB represents combinations of CuAg,
MgCu, MgAg, MgZn, CuZn or AgZn.
Quinary Alloys
[0088] Ca.sub.100-x-y-zAl.sub.xMg.sub.y(A.sub.aB.sub.b).sub.z
[0089] where 27.ltoreq.x.ltoreq.35, 5.ltoreq.y.ltoreq.15,
5.ltoreq.z.ltoreq.15, 0.ltoreq.a,b.ltoreq.100, AB represents
combinations of CuZn or AgZn.
[0090] These alloys are found to exhibit a Tg=180-240.degree. C.,
Tx=200-270.degree. C., and Trg=0.56-0.61 (applicable only for those
alloys that show a glass transition). Typical XRD pattern of the
cast amorphous rods is shown in FIG. 2. Curves of differential
scanning calorimeter (DSC) analysis showing the glass transition,
crystallization and melting behavior are given in FIGS. 3 and 4. It
is interesting to note that binary Ca--Al amorphous alloys possess
the highest thermal stability. However, further introduction of Cu,
Ag, Mg and/or Zn increase the glass formability of this alloy
system. The diameter of the cast rods with a fully amorphous
structure increases from 1 mm for binary alloys to 3 mm for
multinary alloys. The addition of Ag helps to extend the
supercooled liquid region, with .DELTA.T=48.degree. C. for
Ca.sub.60Al.sub.30Ag.sub.10. A number of typical amorphous alloys
are listed in Table 2, together with their Tg (if observable), Tx
and the glass formability characterized by the diameter (in mm) of
the cast rod with a fully amorphous structure.
EXAMPLE 3
Low Al Content Ca--Al-Based Alloys
[0091] The low Al content CaAl alloys are composed of at least four
components. With decreasing the Al content to the range of 5 to 15
atomic percent, and at the same time, mainly increasing Zn content
to replace Al, the designed alloys are given in the following
formula: Ca.sub.xAl.sub.5-15Mg.sub.yZn.sub.zCu.sub.s(Ni).sub.t
[0092] where 50<x<65, 10<y<15, 10<z<20,
0.ltoreq.s<15 and 0.ltoreq.t<10.
[0093] The thermal stability of the obtained amorphous alloys was
decreased when compared to the high Al content alloys, with Tg
ranging from 120 to 150.degree. C. and Tx from 150 to 200.degree.
C. or above. However, the glass formability was greatly improved,
resulting in alloys that can be cast into 9 mm diameter amorphous
rods. FIG. 1 shows a picture of the as-cast 9 mm amorphous rod of
Ca.sub.55Al.sub.10Mg.sub.15Zu.sub.15Cu.sub.5 alloy. FIG. 5 presents
a series of DSC curves of the low Al content CaAl alloys where the
glass transition, crystallization and melting behavior are shown. A
number of typical amorphous alloys are listed in Table 3, together
with their Tg (if observable), Tx and the glass formability
characterized by the diameter (in mm) of the cast rod with a fully
amorphous structure.
[0094] Both high and low Al content Ca--Al alloys possess a low
mass density. The calculated mass density of the alloys ranges from
1.74 to 2.50 gram/cc. The calculation is done by neglecting the
possible volume contraction and expansion effect when alloying
these component elements together.
[0095] Preliminary measurement indicated that the microhardness of
the invention amorphous alloys is in the range 200-240 DPH. The
fracture strength has not been evaluated yet. According to the
empirical rule between the microhardness value and the mechanical
property, the fracture tensile strength is expected to be on the
level of 700-800 MPa. TABLE-US-00002 TABLE 2 Thermal data obtained
from differential thermal analysis (DTA) scans of High Al content
Ca-based bulk amorphous alloys. Calculated Tg Tx Diameter of mass
density Composition (at. %) (.degree. C.) (.degree. C.) amorphous
rod (gram/cc) Ca.sub.66.4Al.sub.33.6 255 267 1 mm 1.74
Ca.sub.55Al.sub.30Cu.sub.15 N/A 206 1 mm 2.17
Ca.sub.60Al.sub.30Cu.sub.10 225 244 1.5 mm 2.00
Ca.sub.55Al.sub.35Cu.sub.10 N/A 244 1 mm 2.05
Ca.sub.65Al.sub.30Cu.sub.5 N/A 242 1 mm 1.85
Ca.sub.63Al.sub.32Cu.sub.5 230 257 2 mm 1.87
Ca.sub.60Al.sub.30Ag.sub.10 210 258 2 mm 2.20
Ca.sub.63Al.sub.32Ag.sub.5 230 254 1.5 mm 1.96
Ca.sub.60Al.sub.30Mg.sub.10 235 250 2 mm 1.74
Ca.sub.60Al.sub.30Zn.sub.10 225 257 1.5 mm 1.99
Ca.sub.55Mg.sub.10Al.sub.30Cu.sub.5 N/A 216 1 mm 2.02
Ca.sub.58Al.sub.32Mg.sub.10 240 266 1.5 mm 1.75
Ca.sub.55Al.sub.30Mg.sub.15 240 262 1 mm 1.75
Ca.sub.58Al.sub.27Mg.sub.15 230 255 1.5 mm 1.73
Ca.sub.56.5Al.sub.28.5Mg.sub.15 230 255 1.5 mm 1.74
Ca.sub.56Al.sub.29Mg.sub.5Cu.sub.10 N/A 206 1 mm 2.01
Ca.sub.53Al.sub.27Mg.sub.10Cu.sub.10 N/A 197 1 mm 2.02
Ca.sub.56.5Al.sub.28.5Mg.sub.10Cu.sub.5 220 247 3 mm 1.87
Ca.sub.56.5Al.sub.28.5Ag.sub.15 210 238 1 mm 2.45
Ca.sub.60Al.sub.30Cu.sub.5Ag.sub.5 215 242 1 mm 2.10
Ca.sub.56.5Al.sub.28.5Ag.sub.10Cu.sub.5 170 194 1 mm 2.35
Ca.sub.62.5Al.sub.31.5Cu.sub.4Ag.sub.2 220 250 1.5 mm 1.93
Ca.sub.60Al.sub.30Ag.sub.8Cu.sub.2 205 248 1.5 mm 2.16
Ca.sub.53Al.sub.27Mg.sub.10Ag.sub.10 205 230 1.5 mm 2.22
Ca.sub.56.5Al.sub.28.5Mg.sub.10Ag.sub.5 215 242 3 mm 1.97
Ca.sub.54.5Al.sub.27.5Mg.sub.10Ag.sub.8 205 238 2 mm 2.12
Ca.sub.55.5Al.sub.29.5Mg.sub.10Ag.sub.5 216 248 2 mm 1.98
Ca.sub.57.5Al.sub.27.5Mg.sub.10Ag.sub.5 220 255 2 mm 1.96
Ca.sub.54.5Al.sub.30.5Mg.sub.10Ag.sub.5 220 257 1.5 mm 1.99
Ca.sub.53.5Al.sub.31.5Mg.sub.10Ag.sub.5 220 257 1.5 mm 2.00
Ca.sub.53Al.sub.27Mg.sub.15Ag.sub.5 210 228 1.5 mm 1.98
Ca.sub.53Al.sub.27Mg.sub.15Cu.sub.5 220 240 1.5 mm 1.88
Ca.sub.53Al.sub.27Mg.sub.13Ag.sub.7 200 224 1 mm 2.07
Ca.sub.53Al.sub.27Mg.sub.17Ag.sub.3 220 245 1 mm 1.88
Ca.sub.56.5Al.sub.28.5Mg.sub.10Zn.sub.5 230 250 1.5 mm 1.87
Ca.sub.56.5Al.sub.28.5Mg.sub.5Zn.sub.5Cu.sub.5 215 235 1 mm 2.00
Ca.sub.56.5Al.sub.28.5Mg.sub.5Zn.sub.5Ag.sub.5 210 240 1.5 mm
2.10
[0096] TABLE-US-00003 TABLE 3 Thermal data obtained from
differential thermal analysis (DTA) scans of Low Al content
Ca-based bulk amorphous alloys. Calculated Tg Tx Diameter of mass
density Composition (at. %) (.degree. C.) (.degree. C.) amorphous
rod (gram/cc) Ca.sub.60Al.sub.5Mg.sub.15Zn.sub.20 127 159 7 mm 2.11
Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.20 137 189 5 mm 2.17
Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.15Cu.sub.5 127 159 9 mm 2.17
Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.10Cu.sub.10 120 138 7 mm 2.18
Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.17Cu.sub.3 135 163 7 mm 2.17
Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.12.5Cu.sub.7.5 116 137 7 mm 2.17
Ca.sub.55Al.sub.10Mg.sub.15Zn.sub.15Ni.sub.5 131 169 7 mm 2.16
Ca.sub.50Al.sub.15Mg.sub.15Zn.sub.15Cu.sub.5 136 189 3 mm 2.22
Ca.sub.55Al.sub.15Mg.sub.10Zn.sub.15Cu.sub.5 141 200 3 mm 2.19
Ca.sub.55Al.sub.15Mg.sub.15Zn.sub.10Cu.sub.5 130 148 3 mm 2.06
* * * * *