U.S. patent application number 12/419787 was filed with the patent office on 2010-10-07 for heat treatable l12 aluminum alloys.
This patent application is currently assigned to UNITED TECHNOLOGIES CORPORATION. Invention is credited to Awadh B. Pandey.
Application Number | 20100252148 12/419787 |
Document ID | / |
Family ID | 42342736 |
Filed Date | 2010-10-07 |
United States Patent
Application |
20100252148 |
Kind Code |
A1 |
Pandey; Awadh B. |
October 7, 2010 |
HEAT TREATABLE L12 ALUMINUM ALLOYS
Abstract
High temperature heat treatable aluminum alloys that can be used
at temperatures from about -420.degree. F. (-251.degree. C.) up to
about 650.degree. F. (343.degree. C.) are described. The alloys are
strengthened by dispersion of particles based on the L1.sub.2
intermetallic compound Al.sub.3X. These alloys comprise aluminum,
magnesium, at least one of silicon, copper and manganese, at least
one of scandium, erbium, thulium, ytterbium, and lutetium, and at
least one of gadolinium, yttrium, zirconium, titanium, hafnium, and
niobium.
Inventors: |
Pandey; Awadh B.; (Jupiter,
FL) |
Correspondence
Address: |
KINNEY & LANGE, P.A.
THE KINNEY & LANGE BUILDING, 312 SOUTH THIRD STREET
MINNEAPOLIS
MN
55415-1002
US
|
Assignee: |
UNITED TECHNOLOGIES
CORPORATION
Hartford
CT
|
Family ID: |
42342736 |
Appl. No.: |
12/419787 |
Filed: |
April 7, 2009 |
Current U.S.
Class: |
148/549 ;
148/439; 148/688 |
Current CPC
Class: |
C22C 21/06 20130101;
C22F 1/043 20130101; C22F 1/047 20130101; C22C 21/08 20130101; C22F
1/057 20130101; C22F 1/05 20130101 |
Class at
Publication: |
148/549 ;
148/688; 148/439 |
International
Class: |
C22C 21/16 20060101
C22C021/16; C22F 1/057 20060101 C22F001/057 |
Claims
1. A heat treatable aluminum alloy comprising: about 0.2 to about
3.0 weight percent magnesium; at least one element selected from
the group comprising about 0.1 to about 2.0 weight percent silicon,
about 0.2 to about 6.5 weight percent copper, and about 0.1 to
about 2.0 weight percent manganese; at least one first element
selected from the group comprising about 0.1 to about 0.5 weight
percent scandium, about 0.1 to about 6.0 weight percent erbium,
about 0.1 to about 10 weight percent thulium, about 0.1 to about
15.0 weight percent ytterbium, and about 0.1 to about 12 weight
percent lutetium; at least one second element selected from the
group comprising about 0.1 to about 4.0 weight percent gadolinium,
about 0.1 to about 4.0 weight percent yttrium, about 0.05 to about
1.0 weight percent zirconium, about 0.05 to about 2.0 weight
percent titanium, about 0.05 to about 2.0 weight percent hafnium,
and about 0.05 to about 1.0 weight percent niobium; and the balance
substantially aluminum.
2. The alloy of claim 1, wherein the alloy comprises an aluminum
solid solution matrix containing a plurality of dispersed Al.sub.3X
second phases having L1.sub.2 structures, wherein X includes at
least one first element and at least one second element.
3. The alloy of claim 1, wherein the alloy comprises an aluminum
solid solution matrix and precipitates including but not limited to
Al.sub.2Cu, Al.sub.2(Cu,Mg), Mg.sub.2Si, and Al.sub.6Mn; a
plurality of dispersed Al.sub.3X second phases having L1.sub.2
structures, wherein X includes at least one first element selected
from the group comprising about 0.1 to about 0.5 weight percent
scandium, about 0.1 to about 6.0 weight percent erbium, about 0.1
to about 10 weight percent thulium, about 0.1 to about 15.0 weight
percent ytterbium, and about 0.1 to about 12 weight percent
lutetium; and at least one second element selected from the group
comprising about 0.1 to about 4.0 weight percent gadolinium, about
0.1 to about 4.0 weight percent yttrium, about 0.05 to about 1.0
weight percent zirconium, about 0.05 to about 2.0 weight percent
titanium, about 0.05 to about 2.0 weight percent hafnium, and about
0.05 to about 1.0 weight percent niobium; and the balance
substantially aluminum.
4. The alloy of claim 1 further including at least one element
selected from the group comprising about 0.1 to about 2.0 weight
percent silicon, about 0.2 to about 6.5 weight percent copper, and
about 0.1 to about 2.0 weight percent manganese.
5. The alloy of claim 1 further comprising at least one of about
0.001 to about 0.1 weight percent sodium, about 0.001 to about 0.1
weight percent calcium, about 0.001 to about 0.1 weight percent
strontium, about 0.001 to about 0.1 weight percent antimony, about
0.001 to about 0.1 weight percent barium, and about 0.001 to about
0.1 weight percent phosphorus.
6. The alloy of claim 1 comprising no more than about 1.0 weight
percent total other elements including impurities.
7. The alloy of claim 1 comprising no more than about 0.1 weight
percent iron, about 0.1 weight percent chromium, about 0.1 weight
percent vanadium, about 0.1 weight percent cobalt, and about 0.1
weight percent nickel.
8. The alloy of claim 1, wherein the amount of silicon ranges from
about 0.2 to about 1.6 weight percent.
9. The alloy of claim 1, which is formed by a process selected from
casting, and subsequent deformation processing, and rapid
solidification processing.
10. The alloy of claim 9, in which the alloy is heat treated by a
solution anneal at a temperature of about 800.degree. F.
(426.degree. C.) to about 1100.degree. F. (593.degree. C.) for
about 30 minutes to four hours, followed by quenching.
11. The alloy of claim 10, wherein the quenching is in liquid, and
wherein the alloy is aged after quenching at a temperature of about
200.degree. F. (9320 C.) to about 600.degree. F. (315.degree. C.)
for about two to forty-eight hours.
12. The heat treatable aluminum alloy of claim 1, wherein the alloy
is capable of being used at temperatures from about -420.degree. F.
(-251.degree. C.) up to about 650.degree. F. (343.degree. C.).
13. A heat treatable aluminum alloy comprising: about 0.2 to about
3.0 weight percent magnesium; at least one element selected from
the group consisting of about 0.1 to about 2.0 weight percent
silicon, about 0.2 to about 6.5 weight percent copper, and about
0.1 to about 2.0 weight percent manganese; an aluminum solid
solution matrix containing a plurality of dispersed Al.sub.3X
second phases having L1.sub.2 structures where X comprises at least
one of scandium, erbium, thulium, ytterbium, lutetium, and at least
one of gadolinium, yttrium, zirconium, titanium, hafnium,
niobium.
14. The alloy of claim 13, wherein the alloy comprises an aluminum
solid solution matrix: precipitates including but not limited to
Al.sub.2Cu, Al.sub.2(Cu,Mg), Mg.sub.2Si, Al.sub.6Mn; and a
plurality of dispersed Al.sub.3X second phases having L1.sub.2
structures where X comprises at least one of scandium, erbium,
thulium, ytterbium, lutetium, and at least one of gadolinium,
yttrium, zirconium, titanium, hafnium, niobium.
15. The alloy of claim 13, wherein the alloy comprises at least one
of: about 0.1 to about 0.5 weight percent scandium, about 0.1 to
about 6.0 weight percent erbium, about 0.1 to about 10 weight
percent thulium, about 0.1 to about 15.0 weight percent ytterbium,
about 0.1 to about 12 weight percent lutetium, and about 0.1 to
about 4.0 weight percent gadolinium, about 0.1 to about 4.0 weight
percent yttrium, about 0.05 to about 1.0 weight percent zirconium,
about 0.05 to about 2.0 weight percent titanium, about 0.05 to
about 2.0 weight percent hafnium, and about 0.05 to about 1.0
weight percent niobium.
16. A method of forming a heat treatable aluminum alloy, the method
comprising: (a) forming a melt comprising: about 0.2 to about 3.0
weight percent magnesium; at least one element selected from the
group comprising about 0.1 to about 2.0 weight percent silicon,
about 0.2 to about 6.5 weight percent copper, and about 0.1 to
about 2.0 weight percent manganese; at least one first element
selected from the group comprising about 0.1 to about 0.5 weight
percent scandium, about 0.1 to about 6.0 weight percent erbium,
about 0.1 to about 10 weight percent thulium, about 0.1 to about
15.0 weight percent ytterbium, and about 0.1 to about 12 weight
percent lutetium; at least one second element selected from the
group comprising about 0.1 to about 4.0 weight percent gadolinium,
about 0.1 to about 4.0 weight percent yttrium, about 0.05 to about
1.0 weight percent zirconium, about 0.05 to about 2.0 weight
percent titanium, about 0.05 to about 2.0 weight percent hafnium,
and about 0.05 to about 1.0 weight percent niobium; and the balance
substantially aluminum; (b) solidifying the melt to form a solid
body; and (c) heat treating the solid body.
17. The method of claim 16 further comprising: refining the
structure of the solid body by deformation processing including but
not limited to these processes:extrusion, forging and rolling.
18. The method of claim 16, wherein solidifying comprises a casting
process.
19. The method of claim 16, wherein solidifying comprises a rapid
solidification process in which the cooling rate is greater than
about 10.sup.3.degree. C./second including at least one of: powder
processing, atomization, melt spinning, splat quenching, spray
deposition, cold spray, plasma spray, laser melting and deposition,
ball milling, and cryomilling.
20. The method of claim 16, wherein the heat treating comprises:
solution heat treatment at about 800.degree. F. (426.degree. C.) to
about 1100.degree. F. (593.degree. C.) for about thirty minutes to
four hours; and quenching; and aging at a temperature of about
200.degree. F. (93.degree. C.) to about 600.degree. F. (315.degree.
C.) for about two to forty eight hours.
Description
CROSS-REFERENCE TO RELATED APPLICATIONS
[0001] This application is related to the following co-pending
applications that were filed on Dec. 9, 2008 herewith and are
assigned to the same assignee: CONVERSION PROCESS FOR HEAT
TREATABLE L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/316,020; A METHOD
FOR FORMING HIGH STRENGTH ALUMINUM ALLOYS CONTAINING L1.sub.2
INTERMETALLIC DISPERSOIDS, Ser. No. 12/316,046; and A METHOD FOR
PRODUCING HIGH STRENGTH ALUMINUM ALLOY POWDER CONTAINING L1.sub.2
INTERMETALLIC DISPERSOIDS, Ser. No. 12/316,047.
[0002] This application is also related to the following co-pending
applications that were filed on Apr. 18, 2008, and are assigned to
the same assignee: L1.sub.2 ALUMINUM ALLOYS WITH BIMODAL AND
TRIMODAL DISTRIBUTION, Ser. No. 12/148,395; DISPERSION STRENGTHENED
L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/148,432; HEAT TREATABLE
L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/148,383; HIGH STRENGTH
L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/148,394; HIGH STRENGTH
L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/148,382; HEAT TREATABLE
L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/148,396; HIGH STRENGTH
L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/148,387; HIGH STRENGTH
ALUMINUM ALLOYS WITH L1.sub.2 PRECIPITATES, Ser. No. 12/148,426;
HIGH STRENGTH L1.sub.2 ALUMINUM ALLOYS, Ser. No. 12/148,459; and
L1.sub.2 STRENGTHENED AMORPHOUS ALUMINUM ALLOYS, Ser. No.
12/148,458.
BACKGROUND
[0003] The present invention relates generally to aluminum alloys
and more specifically to heat treatable aluminum alloys produced by
melt processing and strengthened by L1.sub.2 phase dispersions.
[0004] The combination of high strength, ductility, and fracture
toughness, as well as low density, make aluminum alloys natural
candidates for aerospace and space applications. However, their use
is typically limited to temperatures below about 300.degree. F.
(149.degree. C.) since most aluminum alloys start to lose strength
in that temperature range as a result of coarsening of
strengthening precipitates.
[0005] The development of aluminum alloys with improved elevated
temperature mechanical properties is a continuing process. Some
attempts have included aluminum-iron and aluminum-chromium based
alloys such as Al--Fe--Ce, Al--Fe--V--Si, Al--Fe--Ce--W, and
Al--Cr--Zr--Mn that contain incoherent dispersoids. These alloys,
however, also lose strength at elevated temperatures due to
particle coarsening. In addition, these alloys exhibit ductility
and fracture toughness values lower than other commercially
available aluminum alloys.
[0006] Other attempts have included the development of mechanically
alloyed Al--Mg and Al--Ti alloys containing ceramic dispersoids.
These alloys exhibit improved high temperature strength due to the
particle dispersion, but the ductility and fracture toughness are
not improved.
[0007] U.S. Pat. No. 6,248,453 discloses aluminum alloys
strengthened by dispersed Al.sub.3X L1.sub.2 intermetallic phases
where X is selected from the group consisting of Sc, Er, Lu, Yb,
Tm, and U. The Al.sub.3X particles are coherent with the aluminum
alloy matrix and are resistant to coarsening at elevated
temperatures. The improved mechanical properties of the disclosed
dispersion strengthened L1.sub.2 aluminum alloys are stable up to
572.degree. F. (300.degree. C.). In order to create aluminum alloys
containing fine dispersions of Al.sub.3X L1.sub.2 particles, the
alloys need to be manufactured by expensive rapid solidification
processes with cooling rates in excess of
1.8.times.10.sup.3.degree. F./sec (10.sup.3.degree. C./sec). U.S.
Patent Application Publication No. 2006/0269437 discloses an
aluminum alloy that contains scandium and other elements. While the
alloy is effective at high temperatures, it is not capable of being
heat treated using a conventional age hardening mechanism.
[0008] Heat treatable aluminum alloys strengthened by coherent
L1.sub.2 intermetallic phases produced by standard, inexpensive
melt processing techniques would be useful.
SUMMARY
[0009] The present invention is heat treatable aluminum alloys that
can be cast, wrought, or formed by rapid solidification, and
thereafter heat treated. The alloys can achieve high temperature
performance and can be used at temperatures up to about 650.degree.
F. (343.degree. C.).
[0010] These alloys comprise silicon, magnesium, and an Al.sub.3X
L1.sub.2 dispersoid where X is at least one first element selected
from scandium, erbium, thulium, ytterbium, and lutetium, and at
least one second element selected from gadolinium, yttrium,
zirconium, titanium, hafnium, and niobium. The balance is
substantially aluminum.
[0011] The alloys may also contain, optionally, copper, and have
less than 1.0 weight percent total impurities.
[0012] The alloys are formed by a process selected from casting,
deformation processing and rapid solidification. The alloys are
then heat treated at a temperature of from about 800.degree. F.
(426.degree. C.) to about 1100.degree. F. (593.degree. C.) for
between about 30 minutes and four hours, followed by quenching in
water, and thereafter aged at a temperature from about 200.degree.
F. (93.degree. C.) to about 600.degree. F. (315.degree. C.) for
about two to forty eight hours.
BRIEF DESCRIPTION OF THE DRAWINGS
[0013] FIG. 1 is an aluminum silicon phase diagram.
[0014] FIG. 2 is an aluminum magnesium phase diagram.
[0015] FIG. 3 is an aluminum copper phase diagram.
[0016] FIG. 4 is an aluminum manganese phase diagram.
[0017] FIG. 5 is an aluminum scandium phase diagram.
[0018] FIG. 6 is an aluminum erbium phase diagram.
[0019] FIG. 7 is an aluminum thulium phase diagram.
[0020] FIG. 8 is an aluminum ytterbium phase diagram.
[0021] FIG. 9 is an aluminum lutetium phase diagram
DETAILED DESCRIPTION
[0022] The alloys of this invention are based on the
aluminum-magnesium-silicon and aluminum-magnesium-copper systems.
The aluminum silicon phase diagram is shown in FIG. 1. The binary
system is a simple eutectic alloy system with a eutectic reaction
at 12.5 weight percent silicon and 1077.degree. F. (577.degree.
C.). There is little solubility of silicon in aluminum at
temperatures up to 930.degree. F. (500.degree. C.) and none of
aluminum in silicon. Hypoeutectic alloys with less than 12.6 weight
percent silicon solidify with a microstructure consisting of
primary aluminum grains in a finely divided aluminum/silicon
eutectic matrix phase. Hypereutectic alloys with silicon contents
greater than the eutectic composition solidify with a
microstructure of primary silicon grains in a finely divided
aluminum/silicon eutectic matrix phase. Alloys of this invention
include alloys with the addition of about 0.1 to about 2.0 weight
percent silicon, more preferably about 0.2 to about 1.6 weight
percent silicon, and even more preferably about 0.3 to about 1.4
weight percent silicon.
[0023] The alloys are formed by a process selected from casting,
casting plus deformation processing and rapid solidification.
Following formation the alloys are heat treated at a temperature of
from about 800.degree. F. (425.degree. C.) to about 1100.degree. F.
(593.degree. C.) for between about 30 minutes and four hours,
followed by quenching in a liquid, and thereafter aged at a
temperature from about 200.degree. F. (93.degree. C.) to about
600.degree. F. (315.degree. C.) for about two to about forty-eight
hours. The alloys of this invention are based on the aluminum
magnesium system. The aluminum magnesium phase diagram is shown in
FIG. 2. The binary system is a eutectic alloy system with a
eutectic reaction at 36 weight percent magnesium and 842.degree. F.
(450.degree. C.). Magnesium has maximum solid solubility of 16
weight percent in aluminum at 842.degree. F. (450.degree. C.). The
amount of magnesium in these alloys ranges from about 0.2 to about
3.0 weight percent, more preferably about 0.4 to about 2.0 weight
percent, and even more preferably about 0.5 to about 1.6 weight
percent. The ratio of magnesium to silicon is about 2.5:1, more
preferably about 2:1, and even more preferably about 1.75:1.
[0024] The aluminum copper phase diagram is shown in FIG. 3. The
aluminum copper binary system is a eutectic alloy system with a
eutectic reaction at 31.2 weight percent copper and 1018.degree. F.
(548.2.degree. C.). Copper has maximum solid solubility of 6 weight
percent in aluminum at 1018.degree. F. (548.2.degree. C.) which can
be extended further by rapid solidification processing. Copper
provides a considerable amount of precipitation strengthening in
aluminum by precipitation of fine second phases. The present
invention is focused on hypoeutectic alloy composition ranges. The
amount of copper in these alloys ranges from about 0.2 to about 6.5
weight percent, more preferably about 0.3 to about 6.0 weight
percent, and even more preferably about 0.4 to about 5.0 weight
percent.
[0025] The aluminum manganese phase diagram is shown in FIG. 4. The
aluminum manganese binary system is a eutectic alloy system with a
eutectic reaction at 2.0 weight percent manganese and
1216.4.degree. F. (658.degree. C.). Manganese has maximum solid
solubility of about 2 weight percent in aluminum at 1216.4.degree.
F. (658.degree. C.) which can be extended further by rapid
solidification processing. Manganese provides a considerable amount
of precipitation strengthening in aluminum by precipitation of fine
Al.sub.6Mn second phases. The present invention is focused on
hypoeutectic alloy composition ranges. The amount of manganese in
these alloys ranges from about 0.1 to about 2.0 weight percent,
more preferably about 0.2 to about 1.5 weight percent, and even
more preferably about 0.3 to about 1.0 weight percent.
[0026] Aluminum-magnesium-silicon alloys and
aluminum-copper-magnesium alloys can include either manganese or
silicon or both. Copper is completely soluble in aluminum in the
compositions of the inventive alloys discussed herein. In
aluminum-magnesium-copper alloys, strengthening phases Al.sub.2Cu
(.theta.'), and Al.sub.2CuMg (S') precipitate following a solution
treatment, quench and age process. Aluminum copper and aluminum
magnesium alloys are heat treatable with Al.sub.2Cu (.theta.'),
Al.sub.2CuMg (S') precipitating. Si crystals also precipitate in
aluminum-copper-silicon alloys. Mg.sub.2Si and Si crystals
precipitate in aluminum-magnesium-silicon alloys following a
solution heat treatment, quench, and age process. In
aluminum-copper-magnesium-silicon alloys, strengthening phases are
Al.sub.2Cu (.theta.'), Al.sub.2CuMg (S'), Mg.sub.2Si and Si
crystals following a solution heat treatment, quench, and age
process. Mg.sub.2Al.sub.3 (.beta.) phase precipitates as large
intermetallic particles in high magnesium containing aluminum
alloys which is not desired from a strengthening point of view. The
presence of L1.sub.2 phase prevents formation of .beta. phase in
this material which improves ductility and toughness of material.
The alloys of this invention also contain phases consisting of
aluminum copper solid solutions, aluminum magnesium solid
solutions, and aluminum copper magnesium solid solutions. In the
solid solutions are dispersions of Al.sub.3X having an L1.sub.2
structure where X is at least one first element selected from
scandium, erbium, thulium, ytterbium, and lutetium. Also present is
at least one second element selected from gadolinium, yttrium,
zirconium, titanium, hafnium, and niobium.
[0027] Exemplary aluminum alloys of this invention include, but are
not limited to (in weight percent): [0028] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.1-4)Gd; [0029] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-0.1-6)Er-(0.1-4)Gd; [0030] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.1-4)Gd; [0031] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.1-4)Gd; [0032] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.1-4)Gd; [0033] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.1-4)Y; [0034] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.1-4)Y; [0035] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.1-4)Y; [0036] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.1-4)Y; [0037] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.1-4)Y; [0038] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-1)Zr; [0039] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.05-1)Zr; [0040] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-1)Zr; [0041] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-1)Zr; [0042] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-1)Zr; [0043] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-2)Ti; [0044] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.05-2)Ti; [0045] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-2)Ti; [0046] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-2)Ti; [0047] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-2)Ti; [0048] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-2)Hf; [0049] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.05-2)Hf; [0050] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-2)Hf; [0051] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-2)Hf; [0052] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-2)Hf, [0053] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-1)Nb; [0054] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.05-1)Nb; [0055] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-1)Nb; [0056] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-1)Nb; and [0057] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-1)Nb.
[0058] Examples of alloys similar to those listed are alloys with
the addition of about 0.2 to about 6.5 weight percent Cu, more
preferably alloys with the addition of about 0.3 to about 6.0
weight percent Cu, and even more preferably alloys with the
addition of about 0.4 to about 5 weight percent Cu. Examples of
other alloys similar to the above are those alloys with the
addition of about 0.1 to about 2.0 weight percent Mn, more
preferably alloys with the addition of about 0.2 to about 1.5
weight percent Mn, and even more preferably alloys with the
addition of about 0.3 to about 1.0 weight percent Mn.
[0059] In the inventive aluminum based alloys disclosed herein,
scandium, erbium, thulium, ytterbium, and lutetium are potent
strengtheners that have low diffusivity and low solubility in
aluminum. All these elements form equilibrium Al.sub.3X
intermetallic dispersoids where X is at least one of scandium,
erbium, ytterbium, lutetium, that have an L1.sub.2 structure that
is an ordered face centered cubic structure with the X atoms
located at the corners and aluminum atoms located on the cube faces
of the unit cell.
[0060] Scandium forms Al.sub.3Sc dispersoids that are fine and
coherent with the aluminum matrix. Lattice parameters of aluminum
and Al.sub.3Sc are very close (0.405 nm and 0.410 nm respectively),
indicating that there is minimal or no driving force for causing
growth of the Al.sub.3Sc dispersoids. This low interfacial energy
makes the Al.sub.3Sc dispersoids thermally stable and resistant to
coarsening up to temperatures as high as about 842.degree. F.
(450.degree. C.). Addition of magnesium in solid solution in
aluminum increases the lattice parameter of the aluminum matrix,
and decreases the lattice parameter mismatch further increasing the
resistance of the Al.sub.3Sc to coarsening. Addition of copper
increases the strength of alloys through precipitation of
Al.sub.2Cu (.theta.') and Al.sub.2CuMg (S') phases. In the alloys
of this invention these Al.sub.3Sc dispersoids are made stronger
and more resistant to coarsening at elevated temperatures by adding
suitable alloying elements such as gadolinium, yttrium, zirconium,
titanium, hafnium, niobium, or combinations thereof, that enter
Al.sub.3Sc in solution.
[0061] Erbium forms Al.sub.3Er dispersoids in the aluminum matrix
that are fine and coherent with the aluminum matrix. The lattice
parameters of aluminum and Al.sub.3Er are close (0.405 nm and 0.417
nm respectively), indicating there is minimal driving force for
causing growth of the Al.sub.3Er dispersoids. This low interfacial
energy makes the Al.sub.3Er dispersoids thermally stable and
resistant to coarsening up to temperatures as high as about
842.degree. F. (450.degree. C.). Addition of magnesium in solid
solution in aluminum increases the lattice parameter of the
aluminum matrix, and decreases the lattice parameter mismatch
further increasing the resistance of the Al.sub.3Er to coarsening.
Addition of copper increases the strength of alloys through
precipitation of Al.sub.2Cu (.theta.') and Al.sub.2CuMg (S')
phases. In the alloys of this invention, these Al.sub.3Er
dispersoids are made stronger and more resistant to coarsening at
elevated temperatures by adding suitable alloying elements such as
gadolinium, yttrium, zirconium, titanium, hafnium, niobium, or
combinations thereof that enter Al.sub.3Er in solution.
[0062] Thulium forms metastable Al.sub.3Tm dispersoids in the
aluminum matrix that are fine and coherent with the aluminum
matrix. The lattice parameters of aluminum and Al.sub.3Tm are close
(0.405 nm and 0.420 nm respectively), indicating there is minimal
driving force for causing growth of the Al.sub.3Tm dispersoids.
This low interfacial energy makes the Al.sub.3Tm dispersoids
thermally stable and resistant to coarsening up to temperatures as
high as about 842.degree. F. (450.degree. C.). Addition of
magnesium in solid solution in aluminum increases the lattice
parameter of the aluminum matrix and decreases the lattice
parameter mismatch further increasing the resistance to coarsening
of the dispersoid. Addition of copper increases the strength of
alloys through precipitation of Al.sub.2Cu (.theta.') and
Al.sub.2CuMg (S') phases. In the alloys of this invention these
Al.sub.3Tm dispersoids are made stronger and more resistant to
coarsening at elevated temperatures by adding suitable alloying
elements such as gadolinium, yttrium, zirconium, titanium, hafnium,
niobium, or combinations thereof that enter Al.sub.3Tm in
solution.
[0063] Ytterbium forms Al.sub.3Yb dispersoids in the aluminum
matrix that are fine and coherent with the aluminum matrix. The
lattice parameters of Al and Al.sub.3Yb are close (0.405 nm and
0.420 nm respectively), indicating there is minimal driving force
for causing growth of the Al.sub.3Yb dispersoids. This low
interfacial energy makes the Al.sub.3Yb dispersoids thermally
stable and resistant to coarsening up to temperatures as high as
about 842.degree. F. (450.degree. C.). Addition of magnesium in
solid solution in aluminum increases the lattice parameter of the
aluminum matrix and decreases the lattice parameter mismatch
further increasing the resistance to coarsening of the Al.sub.3Yb.
Addition of copper increases the strength of alloys through
precipitation of Al.sub.2Cu (.theta.') and Al.sub.2CuMg (S')
phases. In the alloys of this invention, these Al.sub.3Yb
dispersoids are made stronger and more resistant to coarsening at
elevated temperatures by adding suitable alloying elements such as
gadolinium, yttrium, zirconium, titanium, hafnium, niobium, or
combinations thereof that enter Al.sub.3Yb in solution.
[0064] Lutetium forms Al.sub.3Lu dispersoids in the aluminum matrix
that are fine and coherent with the aluminum matrix. The lattice
parameters of Al and Al.sub.3Lu are close (0.405 nm and 0.419 nm
respectively), indicating there is minimal driving force for
causing growth of the Al.sub.3Lu dispersoids. This low interfacial
energy makes the Al.sub.3Lu dispersoids thermally stable and
resistant to coarsening up to temperatures as high as about
842.degree. F. (450.degree. C.). Addition of magnesium in solid
solution in aluminum increases the lattice parameter of the
aluminum matrix and decreases the lattice parameter mismatch
further increasing the resistance to coarsening of Al.sub.3Lu.
Addition of copper increases the strength of alloys through
precipitation of Al.sub.2Cu (.theta.') and Al.sub.2CuMg (S')
phases. In the alloys of this invention, these Al.sub.3Lu
dispersoids are made stronger and more resistant to coarsening at
elevated temperatures by adding suitable alloying elements such as
gadolinium, yttrium, zirconium, titanium, hafnium, niobium, or
mixtures thereof that enter Al.sub.3Lu in solution.
[0065] Gadolinium forms metastable Al.sub.3Gd dispersoids in the
aluminum matrix that have an L1.sub.2 structure in the metastable
condition. The Al.sub.3Gd dispersoids are stable up to temperatures
as high as about 842.degree. F. (450.degree. C.) due to their low
diffusivity in aluminum. The Al.sub.3Gd dispersoids have a
D0.sub.19 structure in the equilibrium condition. Despite its large
atomic size, gadolinium has fairly high solubility in the Al.sub.3X
intermetallic dispersoids (where X is scandium, erbium, thulium,
ytterbium or lutetium). Gadolinium can substitute for the X atoms
in Al.sub.3X intermetallic, thereby forming an ordered L1.sub.2
phase which results in improved thermal and structural
stability.
[0066] Yttrium forms metastable Al.sub.3Y dispersoids in the
aluminum matrix that have an L1.sub.2 structure in the metastable
condition and a D0.sub.19 structure in the equilibrium condition.
The metastable Al.sub.3Y dispersoids have a low diffusion
coefficient which makes them thermally stable and highly resistant
to coarsening. Yttrium has a high solubility in the Al.sub.3X
intermetallic dispersoids allowing large amounts of yttrium to
substitute for X in the Al.sub.3X L1.sub.2 dispersoids which
results in improved thermal and structural stability.
[0067] Zirconium forms Al.sub.3Zr dispersoids in the aluminum
matrix that have an L1.sub.2 structure in the metastable condition
and D0.sub.23 structure in the equilibrium condition. The
metastable Al.sub.3Zr dispersoids have a low diffusion coefficient
which makes them thermally stable and highly resistant to
coarsening. Zirconium has a high solubility in the Al.sub.3X
dispersoids allowing large amounts of zirconium to substitute for X
in the Al.sub.3X dispersoids, which results in improved thermal and
structural stability.
[0068] Titanium forms Al.sub.3Ti dispersoids in the aluminum matrix
that have an L1.sub.2 structure in the metastable condition and
D0.sub.22 structure in the equilibrium condition. The metastable
Al.sub.3Ti dispersoids have a low diffusion coefficient which makes
them thermally stable and highly resistant to coarsening. Titanium
has a high solubility in the Al.sub.3X dispersoids allowing large
amounts of titanium to substitute for X in the Al.sub.3X
dispersoids, which results in improved thermal and structural
stability.
[0069] Hafnium forms metastable Al.sub.3Hf dispersoids in the
aluminum matrix that have an L1.sub.2 structure in the metastable
condition and a D0.sub.23 structure in the equilibrium condition.
The Al.sub.3Hf dispersoids have a low diffusion coefficient, which
makes them thermally stable and highly resistant to coarsening.
Hafnium has a high solubility in the Al.sub.3X dispersoids allowing
large amounts of hafnium to substitute for scandium, erbium,
thulium, ytterbium, and lutetium in the above mentioned Al.sub.3X
dispersoids, which results in stronger and more thermally stable
dispersoids.
[0070] Niobium forms metastable Al.sub.3Nb dispersoids in the
aluminum matrix that have an L1.sub.2 structure in the metastable
condition and a D0.sub.22 structure in the equilibrium condition.
Niobium has a lower solubility in the Al.sub.3X dispersoids than
hafnium or yttrium, allowing relatively lower amounts of niobium
than hafnium or yttrium to substitute for X in the Al.sub.3X
dispersoids. Nonetheless, niobium can be very effective in slowing
down the coarsening kinetics of the Al.sub.3X dispersoids because
the Al.sub.3Nb dispersoids are thermally stable. The substitution
of niobium for X in the above mentioned Al.sub.3X dispersoids
results in stronger and more thermally stable dispersoids.
[0071] Al.sub.3X L1.sub.2 precipitates improve elevated temperature
mechanical properties in aluminum alloys for two reasons. First,
the precipitates are ordered intermetallic compounds. As a result,
when the particles are sheared by glide dislocations during
deformation, the dislocations separate into two partial
dislocations separated by an anti-phase boundary on the glide
plane. The energy to create the anti-phase boundary is the origin
of the strengthening. Second, the cubic L1.sub.2 crystal structure
and lattice parameter of the precipitates are closely matched to
the aluminum solid solution matrix. This results in a lattice
coherency at the precipitate/matrix boundary that resists
coarsening. The lack of an interphase boundary results in a low
driving force for particle growth and resulting elevated
temperature stability. Alloying elements in solid solution in the
dispersed strengthening particles and in the aluminum matrix that
tend to decrease the lattice mismatch between the matrix and
particles will tend to increase the strengthening and elevated
temperature stability of the alloy.
[0072] The amount of scandium present in the alloys of this
invention if any may vary from about 0.1 to about 0.5 weight
percent, more preferably from about 0.1 to about 0.35 weight
percent, and even more preferably from about 0.1 to about 0.25
weight percent. The Al--Sc phase diagram shown in FIG. 2 indicates
a eutectic reaction at about 0.5 weight percent scandium at about
1219.degree. F. (659.degree. C.) resulting in a solid solution of
scandium and aluminum and Al.sub.3Sc dispersoids. Aluminum alloys
with less than 0.5 weight percent scandium can be quenched from the
melt to retain scandium in solid solution that may precipitate as
dispersed L1.sub.2 intermetallic Al.sub.3Sc following an aging
treatment. Alloys with scandium in excess of the eutectic
composition (hypereutectic alloys) can only retain scandium in
solid solution by rapid solidification processing (RSP) where
cooling rates are in excess of about 10.sup.3.degree.
C./second.
[0073] The amount of erbium present in the alloys of this
invention, if any, may vary from about 0.1 to about 6.0 weight
percent, more preferably from about 0.1 to about 4 weight percent,
and even more preferably from about 0.2 to 2 weight percent. The
Al--Er phase diagram shown in FIG. 3 indicates a eutectic reaction
at about 6 weight percent erbium at about 1211.degree. F.
(655.degree. C.). Aluminum alloys with less than about 6 weight
percent erbium can be quenched from the melt to retain erbium in
solid solutions that may precipitate as dispersed L1.sub.2
intermetallic Al.sub.3Er following an aging treatment. Alloys with
erbium in excess of the eutectic composition can only retain erbium
in solid solution by rapid solidification processing (RSP) where
cooling rates are in excess of about 10.sup.3.degree. C./second.
Alloys with erbium in excess of the eutectic composition
(hypereutectic alloys) cooled normally will have a microstructure
consisting of relatively large Al.sub.3Er dispersoid in a finely
divided aluminum-Al.sub.3Er eutectic phase matrix.
[0074] The amount of thulium present in the alloys of this
invention, if any, may vary from about 0.1 to about 10 weight
percent, more preferably from about 0.2 to about 6 weight percent,
and even more preferably from about 0.2 to about 4 weight percent.
The Al--Tm phase diagram shown in FIG. 4 indicates a eutectic
reaction at about 10 weight percent thulium at about 1193.degree.
F. (645.degree. C.). Thulium forms metastable Al.sub.3Tm
dispersoids in the aluminum matrix that have an L1.sub.2 structure
in the equilibrium condition. The Al.sub.3Tm dispersoids have a low
diffusion coefficient which makes them thermally stable and highly
resistant to coarsening. Aluminum alloys with less than 10 weight
percent thulium can be quenched from the melt to retain thulium in
solid solution that may precipitate as dispersed metastable
L1.sub.2 intermetallic Al.sub.3Tm following an aging treatment.
Alloys with thulium in excess of the eutectic composition can only
retain Tm in solid solution by rapid solidification processing
(RSP) where cooling rates are in excess of about 10.sup.3.degree.
C./second.
[0075] The amount of ytterbium present in the alloys of this
invention, if any, may vary from about 0.1 to about 15 weight
percent more preferably from about 0.2 to about 8 weight percent,
and even more preferably from about 0.2 to about 4 weight percent.
The Al--Yb phase diagram shown in FIG. 5 indicates a eutectic
reaction at about 21 weight percent ytterbium at about 1157.degree.
F. (625.degree. C.). Aluminum alloys with less than about 21 weight
percent ytterbium can be quenched from the melt to retain ytterbium
in solid solution that may precipitate as dispersed L1.sub.2
intermetallic Al.sub.3Yb following an aging treatment. Alloys with
ytterbium in excess of the eutectic composition can only retain
ytterbium in solid solution by rapid solidification processing
(RSP) where cooling rates are in excess of about 10.sup.3.degree.
C./second.
[0076] The amount of lutetium present in the alloys of this
invention, if any, may vary from about 0.1 to about 12 weight
percent, more preferably from 0.2 to about 8 weight percent, and
even more preferably from about 0.2 to about 4 weight percent. The
Al--Lu phase diagram shown in FIG. 6 indicates a eutectic reaction
at about 11.7 weight percent Lu at about 1202.degree. F.
(650.degree. C.). Aluminum alloys with less than about 11.7 weight
percent lutetium can be quenched from the melt to retain Lu in
solid solution that may precipitate as dispersed L1.sub.2
intermetallic Al.sub.3Lu following an aging treatment. Alloys with
Lu in excess of the eutectic composition can only retain Lu in
solid solution by rapid solidification processing (RSP) where
cooling rates are in excess of about 10.sup.3.degree.
C./second.
[0077] The amount of gadolinium present in the alloys of this
invention, if any, may vary from about 0.1 to about 4 weight
percent, more preferably from 0.2 to about 2 weight percent, and
even more preferably from about 0.5 to about 2 weight percent.
[0078] The amount of yttrium present in the alloys of this
invention, if any, may vary from about 0.1 to about 4 weight
percent, more preferably from 0.2 to about 2 weight percent, and
even more preferably from about 0.5 to about 2 weight percent.
[0079] The amount of zirconium present in the alloys of this
invention, if any, may vary from about 0.05 to about 1 weight
percent, more preferably from 0.1 to about 0.75 weight percent, and
even more preferably from about 0.1 to about 0.5 weight
percent.
[0080] The amount of titanium present in the alloys of this
invention, if any, may vary from about 0.05 to 2 about weight
percent, more preferably from 0.1 to about 1 weight percent, and
even more preferably from about 0.1 to about 0.5 weight
percent.
[0081] The amount of hafnium present in the alloys of this
invention, if any, may vary from about 0.05 to about 2 weight
percent, more preferably from 0.1 to about 1 weight percent, and
even more preferably from about 0.1 to about 0.5 weight
percent.
[0082] The amount of niobium present in the alloys of this
invention, if any, may vary from about 0.05 to about 1 weight
percent, more preferably from 0.1 to about 0.75 weight percent, and
even more preferably from about 0.1 to about 0.5 weight
percent.
[0083] In order to have the best properties for the alloys of this
invention, it is desirable to limit the amount of other elements.
Specific elements that should be reduced or eliminated include no
more than about 0.1 weight percent iron, 0.1 weight percent
chromium, 0.1 weight percent vanadium, 0.1 weight percent cobalt,
and 0.1 weight percent nickel. The total quantity of additional
elements should not exceed about 1% by weight, including the above
listed elements.
[0084] Other additions in the inventive alloys include at least one
of about 0.001 weight percent to about 0.10 weight percent sodium,
about 0.001 weight percent to about 0.10 weight percent calcium,
about 0.001 to about 0.10 weight percent strontium, about 0.001 to
about 0.10 weight percent antimony, 0.001 to 0.10 weight percent
barium and about 0.001 to about 0.10 weight percent phosphorus.
These are added to refine the microstructure of the eutectic phase
and the primary silicon particle morphology and size.
[0085] These aluminum alloys may be made by any and all
consolidation and fabrication processes known to those in the art
such as casting (without further deformation), deformation
processing (wrought processing), rapid solidification processing,
forging, extrusion, rolling, die forging, powder metallurgy and
others. The rapid solidification process should have a cooling rate
greater than about 10.sup.3.degree. C./second including but not
limited to powder processing, atomization, melt spinning, splat
quenching, spray deposition, cold spray, plasma spray, laser
melting and deposition, ball milling and cryomilling.
[0086] Preferred exemplary aluminum alloys of this invention
include, but are not limited to (in weight percent): [0087] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg 0.1-0.35)Sc-(0.2-2)Gd; [0088] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-4)Er-(0.2-2)Gd; [0089] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.2-2)Gd; [0090] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.2-2)Gd; [0091] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.2-2)Gd; [0092] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.2-2)Y; [0093] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-4)Er-(0.2-2)Y; [0094] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.2-2)Y; [0095] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.2-2)Y; [0096] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.2-2)Y; [0097] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.1-0.75)Zr; [0098] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-4)Er-(0.1-0.75)Zr; [0099] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-0.75)Zr; [0100] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-0.75)Zr; [0101] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-0.75)Zr; [0102] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg (0.1-0.35)Sc-(0.1-1)Ti; [0103] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg (0.1-4)Er-(0.1-1)Ti; [0104] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-1)Ti; [0105] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-1)Ti; [0106] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-1)Ti; [0107] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.1-1)Hf; [0108] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg (0.1-4)Er-(0.1-1)Hf; [0109] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-1)Hf; [0110] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-1)Hf; [0111] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-1)Hf; [0112] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.1-0.75)Nb; [0113] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.75)Nb; [0114] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-0.75)Nb; [0115] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-0.75)Nb; and [0116] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-0.75)Nb.
[0117] Examples of alloys similar to those listed above are alloys
with the addition of about 0.2 to about 6.5 weight percent Cu, more
preferably alloys with the addition of about 0.3 to about 6.0
weight percent Cu, and even more preferably alloys with the
addition of about 0.4 to about 5 weight percent Cu. Examples of
other alloys similar to the above are alloys with the addition of
about 0.1 to about 2.0 weight percent Mn, more preferably alloys
with the addition of about 0.2 to about 1.5 weight percent Mn, and
even more preferably alloys with the addition of about 0.3 to about
1.0 weight percent Mn.
[0118] Even more preferred exemplary aluminum alloys of this
invention include, but are not limited to (in weight percent):
[0119] about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.5-2)Gd;
[0120] about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.5-2)Gd; [0121]
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.5-2)Gd; [0122] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.5-2)Gd; [0123] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.5-2)Gd; [0124] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.5-2)Y; [0125] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.5-2)Y; [0126] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.5-2)Y; [0127] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.5-2)Y; [0128] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.5-2)Y; [0129] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Zr; [0130] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Zr; [0131] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Zr; [0132] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Zr; [0133] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Zr; [0134] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Ti; [0135] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Ti; [0136] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Ti; [0137] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Ti; [0138] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Ti; [0139] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Hf; [0140] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Hf; [0141] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Hf; [0142] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Hf; [0143] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Hf; [0144] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Nb; [0145] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Nb; [0146] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Nb; [0147] about
Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Nb; and [0148] about
Al-(-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Nb.
[0149] Examples of alloys similar to those listed above are alloys
with the addition of about 0.2 to about 6.5 weight percent Cu, more
preferably alloys with the addition of about 0.3 to about 6.0
weight percent Cu, and even more preferably alloys with the
addition of about 0.4 to about 5 weight percent Cu. Examples of
other alloys similar to these are alloys with the addition of about
0.1 to about 2.0 weight percent Mn, more preferably alloys with the
addition of about 0.2 to about 1.5 weight percent Mn, and even more
preferably alloys with the addition of about 0.3 to about 1.0
weight percent Mn.
[0150] Exemplary aluminum alloys of this invention include, but are
not limited to (in weight percent): [0151] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.1-4)Gd; [0152] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg 0.1-6)Er-(0.1-4)Gd; [0153] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-10)Tm-(0.1-4)Gd; [0154] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-15)Yb-(0.1-4)Gd; [0155] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-12)Lu-(0.1-4)Gd; [0156] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.1-4)Y; [0157] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-6)Er-(0.1-4)Y; [0158] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-10)Tm-(0.1-4)Y; [0159] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-15)Yb-(0.1-4)Y; [0160] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-12)Lu-(0.1-4)Y; [0161] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-1)Zr; [0162] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-6)Er-(0.05-1)Zr; [0163] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-1)Zr; [0164] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-1)Zr; [0165] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-1)Zr; [0166] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-2)Ti; [0167] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-6)Er-(0.05-2)Ti; [0168] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-2)Ti; [0169] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-2)Ti; [0170] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-2)Ti; [0171] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-2)Hf; [0172] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-6)Er-(0.05-2)Hf; [0173] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-2)Hf; [0174] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-2)Hf; [0175] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-2)Hf; [0176] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.5)Sc-(0.05-1)Nb; [0177] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-6)Er-(0.05-1)Nb; [0178] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-1)Nb; [0179] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-1)Nb; and [0180] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-1)Nb.
[0181] Examples of alloys similar to those listed above are alloys
with the addition of about 0.1 to about 2.0 weight percent Si, more
preferably alloys with the addition of about 0.2 to about 1.6
weight percent Si, and even more preferably alloys with the
addition of about 0.3 to about 1.4 weight percent Si. Examples of
other alloys similar to these are alloys with the addition of about
0.1 to about 2.0 weight percent Mn, more preferably alloys with the
addition of about 0.2 to about 1.5 weight percent Mn, and even more
preferably alloys with the addition of about 0.3 to about 1.0
weight percent Mn.
[0182] Preferred exemplary aluminum alloys of this invention
include, but are not limited to (in weight percent): [0183] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg 0.1-0.35)Sc-(0.2-2)Gd; [0184] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-4)Er-(0.2-2)Gd; [0185] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-6)Tm-(0.2-2)Gd; [0186] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Yb-(0.2-2)Gd; [0187] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Lu-(0.2-2)Gd; [0188] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.2-2)Y; [0189] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-4)Er-(0.2-2)Y; [0190] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-6)Tm-(0.2-2)Y; [0191] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Yb-(0.2-2)Y; [0192] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Lu-(0.2-2)Y; [0193] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.1-0.75)Zr; [0194] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-4)Er-(0.1-0.75)Zr; [0195] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-0.75)Zr; [0196] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-0.75)Zr; [0197] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-0.75)Zr; [0198] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg (0.1-0.35)Sc-(0.1-1)Ti; [0199] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg (0.1-4)Er-(0.1-1)Ti; [0200] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-1)Ti; [0201] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-1)Ti; [0202] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-1)Ti; [0203] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.1-1)Hf; [0204] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-4)Er-(0.1-1)Hf; [0205] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-1)Hf; [0206] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-1)Hf; [0207] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-1)Hf; [0208] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.35)Sc-(0.1-0.75)Nb; [0209] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.75)Nb; [0210] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-0.2-6)Tm-(0.1-0.75)Nb; [0211] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-0.75)Nb; and [0212] about
Al-(-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-0.75)Nb.
[0213] Examples of alloys similar to those listed above are alloys
with the addition of about 0.1 to about 2.0 weight percent Si, more
preferably alloys with the addition of about 0.2 to about 1.6
weight percent Si, and even more preferably alloys with the
addition of about 0.3 to about 1.4 weight percent Si. Examples of
other alloys similar to these are alloys with the addition of about
0.1 to about 2.0 weight percent Mn, more preferably alloys with the
addition of about 0.2 to about 1.5 weight percent Mn, and even more
preferably alloys with the addition of about 0.3 to about 1.0
weight percent Mn.
[0214] Even more preferred exemplary aluminum alloys of this
invention include, but are not limited to (in weight percent):
[0215] about Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.5-2)Gd;
[0216] about Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-2)Er-(0.5-2)Gd; [0217]
about Al-(0.2-6.5)Cu-(0.2-3.0)Mg-0.2-4)Tm-(0.5-2)Gd; [0218] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Yb-(0.5-2)Gd; [0219] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Lu-(0.5-2)Gd; [0220] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.5-2)Y; [0221] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-2)Er-(0.5-2)Y; [0222] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Tm-(0.5-2)Y; [0223] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Yb-(0.5-2)Y; [0224] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Lu-(0.5-2)Y; [0225] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Zr; [0226] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Zr; [0227] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Zr; [0228] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Zr; [0229] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Zr; [0230] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Ti; [0231] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Ti; [0232] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Ti; [0233] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Ti; [0234] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Ti; [0235] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Hf; [0236] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Hf; [0237] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Hf; [0238] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Hf; [0239] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Hf; [0240] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.1-0.25)Sc-(0.1-0.5)Nb; [0241] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Nb; [0242] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Nb; [0243] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Nb; and [0244] about
Al-(0.2-6.5)Cu-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Nb.
[0245] Examples of alloys similar to those listed above are alloys
with the addition of about 0.1 to about 2.0 weight percent Si, more
preferably alloys with the addition of about 0.2 to about 1.6
weight percent Si, and even more preferably alloys with the
addition of about 0.3 to about 1.4 weight percent Si. Examples of
other alloys similar to these are alloys with the addition of about
0.1 to about 2.0 weight percent Mn, more preferably alloys with the
addition of about 0.2 to about 1.5 weight percent Mn, and even more
preferably alloys with the addition of about 0.3 to about 1.0
weight percent Mn.
[0246] Although the present invention has been described with
reference to preferred embodiments, workers skilled in the art will
recognize that changes may be made in form and detail without
departing from the spirit and scope of the invention.
* * * * *