U.S. patent application number 12/148387 was filed with the patent office on 2009-10-22 for high strength l12 aluminum alloys.
This patent application is currently assigned to United Technologies Corporation. Invention is credited to Awadh B. Pandey.
Application Number | 20090263273 12/148387 |
Document ID | / |
Family ID | 40636893 |
Filed Date | 2009-10-22 |
United States Patent
Application |
20090263273 |
Kind Code |
A1 |
Pandey; Awadh B. |
October 22, 2009 |
High strength 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,
zinc, magnesium, at least one of scandium, erbium, thulium,
ytterbium, and lutetium; and at least one of gadolinium, yttrium,
zirconium, titanium, hafnium, and niobium. Copper is an optional
alloying element.
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: |
40636893 |
Appl. No.: |
12/148387 |
Filed: |
April 18, 2008 |
Current U.S.
Class: |
420/532 ;
148/437; 420/541 |
Current CPC
Class: |
C22C 21/10 20130101;
C22F 1/053 20130101 |
Class at
Publication: |
420/532 ;
420/541; 148/437 |
International
Class: |
C22C 21/00 20060101
C22C021/00 |
Claims
1. A heat treatable aluminum alloy comprising: about 3.0 to about
12.0 weight percent zinc; about 0.5 to about 3.5 weight percent
magnesium; 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 10.0
weight percent thulium, about 0.1 to about 15.0 weight percent
ytterbium, and about 0.1 to about 12.0 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, further comprising about 0.2 to 3.0 weight
percent copper.
4. The alloy of claim 1, further comprising at least one of about
0.001 weight percent to about 0.1 weight percent sodium, about
0.001 weight percent to about 0.1 weight calcium, about 0.001
weight percent to about 0.1 weight percent strontium, about 0.001
weight percent to about 0.1 weight percent antimony, about 0.001
weight percent to about 0.1 weight percent barium and about 0.001
weight percent to about 0.1 weight percent phosphorus.
5. The alloy of claim 1, comprising no more than about 1.0 weight
percent total other elements including impurities.
6. 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 manganese, about 0.1 weight percent vanadium, about 0.1
weight percent cobalt, and about 0.1 weight percent nickel.
7. The alloy of claim 1, wherein the alloy is formed by a process
selected from casting, deformation processing, and rapid
solidification processing.
8. The alloy of claim 7, wherein the alloy is heat treated after
forming.
9. The alloy of claim 8, wherein 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.
10. The alloy of claim 9, wherein the quenching is in liquid.
11. The alloy of claim 10, wherein the alloy is aged after
quenching.
12. The alloy of claim 11, wherein the aging occurs at a
temperature of about 200.degree. F. (93.degree. C.) to about
600.degree. F. (316.degree. C.) for about two to forty-eight
hours.
13. 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.).
14. A heat treatable aluminum alloy comprising: about 3.0 to about
12.0 weight percent zinc; about 0.5 to about 3.5 weight percent
magnesium; 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 and lutetium, and at least one of gadolinium, yttrium,
zirconium, titanium, hafnium and niobium; and the balance
substantially aluminum.
15. The alloy of claim 14 further comprising about 0.2 to about 3.0
weight percent copper.
16. The alloy of claim 14, 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 10.0 weight
percent thulium, about 0.1 to about 15.0 weight percent ytterbium,
about 0.1 to about 12.0 weight percent lutetium, 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.
17. A method of forming a heat treatable aluminum alloy, the method
comprising: (a) forming a melt comprising: about 3.0 to about 12.0
weight percent zinc; about 0.5 to about 3.5 weight percent
magnesium; 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 10.0
weight percent thulium, about 0.1 to about 15.0 weight percent
ytterbium, and about 0.1 to about 12.0 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.
18. The method of claim 17, wherein the melt further comprises
about 0.2 to about 3.0 weight percent copper.
19. The method of claim 17, further comprising: refining the
structure of the solid body by deformation processing comprising at
least one of: extrusion, forging and rolling.
20. The method of claim 17, wherein solidifying comprises a casting
process.
21. The method of claim 17, wherein solidifying comprises a rapid
solidification process in which the cooling rate is greater than
about 10.sup.3.degree. C./second and comprising at least one of:
powder processing, atomization, melt spinning, splat quenching,
spray deposition, cold spray, plasma spray, laser melting, laser
deposition, ball milling and cryomilling.
22. The method of claim 17 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; quenching; and aging at about 200.degree. F.
(93.degree. C.) to about 600.degree. F. (316.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 are filed on even date herewith and are assigned
to the same assignee: L1.sub.2 ALUMINUM ALLOYS WITH BIMODAL AND
TRIMODAL DISTRIBUTION, Ser. No. ______, Attorney Docket No.
PA0006933U-U73.12-325KL; DISPERSION STRENGTHENED L1.sub.2 ALUMINUM
ALLOYS, Ser. No. ______, Attorney Docket No.
PA0006932U-U73.12-326KL; HEAT TREATABLE L1.sub.2 ALUMINUM ALLOYS,
Ser. No. ______, Attorney Docket No. PA0006931U-U73.12-327KL; HIGH
STRENGTH L1.sub.2 ALUMINUM ALLOYS, Ser. No. ______, Attorney Docket
No. PA0006929U-U73.12-329KL; HIGH STRENGTH L1.sub.2 ALUMINUM
ALLOYS, Ser. No. ______, Attorney Docket No.
PA0006928U-U73.12-330KL; HEAT TREATABLE L1.sub.2 ALUMINUM ALLOYS,
Ser. No. ______, Attorney Docket No. PA0006927U-U73.12-331KL; HIGH
STRENGTH ALUMINUM ALLOYS WITH L1.sub.2 PRECIPITATES, Ser. No.
______, Attorney Docket No. PA0006924U-U73.12-334KL; HIGH STRENGTH
L1.sub.2 ALUMINUM ALLOYS, Ser. No. ______, Attorney Docket No.
PA0006923U-U73.12-335KL; and L1.sub.2 STRENGTHENED AMORPHOUS
ALUMINUM ALLOYS, Ser. No. ______, Attorney Docket No.
PA0001359U-U73.12-336KL.
BACKGROUND
[0002] 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.
[0003] 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.
[0004] 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.
[0005] 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.
[0006] 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 F/sec
(10.sup.3 C/sec). U.S. Patent Application Publication No.
2006/0269437 A1 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.
[0007] Heat treatable aluminum alloys strengthened by coherent
L1.sub.2 intermetallic phases produced by standard, inexpensive
melt processing techniques would be useful.
SUMMARY
[0008] 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.).
[0009] These alloys comprise zinc, 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. The alloys may also include copper.
[0010] The alloys have less than 1.0 weight percent total
impurities.
[0011] 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. (260.degree. C.) for
about two to about forty-eight hours.
BRIEF DESCRIPTION OF THE DRAWINGS
[0012] FIG. 1 is an aluminum zinc phase diagram.
[0013] FIG. 2 is an aluminum copper phase diagram.
[0014] FIG. 3 is an aluminum magnesium phase diagram.
[0015] FIG. 4 is an aluminum scandium phase diagram.
[0016] FIG. 5 is an aluminum erbium phase diagram.
[0017] FIG. 6 is an aluminum thulium phase diagram.
[0018] FIG. 7 is an aluminum ytterbium phase diagram.
[0019] FIG. 8 is an aluminum lutetium phase diagram.
DETAILED DESCRIPTION
[0020] The alloys of this invention are based on the aluminum,
zinc, magnesium system. The amount of zinc in these alloys ranges
from about 3.0 to about 12.0 weight percent, more preferably about
4.0 to about 10.0 weight percent, and even more preferably about
5.0 to about 9.0 weight percent. The amount of magnesium in these
alloys ranges from about 0.5 to about 3.5 weight percent, more
preferably about 1.0 to about 3.0 weight percent, and even more
preferably about 1.5 to about 3.0 weight percent. The amount of
copper in these alloys ranges from about 0.2 to about 3.0 weight
percent, more preferably about 0.5 to about 2.5 weight percent, and
even more preferably about 1.0 to about 2.5 weight percent.
[0021] The aluminum zinc phase diagram is shown in FIG. 1. The
aluminum zinc binary system is a eutectic alloy system involving a
monotectoid reaction and a miscibility gap in the solid state.
There is a eutectic reaction at 94 weight percent zinc at
717.8.degree. F. (381.degree. C.). Zinc has maximum solid
solubility of 83.1 weight percent in aluminum at 717.8.degree. F.
(381.degree. C.) which can be extended by rapid solidification
processing. The solubility of zinc in aluminum decreases with a
decrease in temperature. Zinc provides significant amount of
precipitation strengthening in aluminum by precipitation of fine
second phases. The present invention is focused on hypoeutectic
alloy composition ranges. Decomposition of the supersaturated solid
solution of zinc in aluminum gives rise to spherical and
ellipsoidal GP zones; precipitates with rhombohedral structure
which are coherent with aluminum matrix and an incoherent
(.alpha.'Al).
[0022] The aluminum copper phase diagram is shown in FIG. 2. The
aluminum copper binary system is a eutectic alloy system with a
eutectic reaction at 31.2 weight percent magnesium 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 considerable amounts of precipitation strengthening
in aluminum by precipitation of fine second phases. The present
invention is focused on hypoeutectic alloy composition ranges.
[0023] The aluminum magnesium phase diagram is shown in FIG. 3. 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.) which can extended
further by rapid solidification processing. Magnesium provides
substantial solid solution strengthening in aluminum. In addition,
magnesium provides precipitation strengthening through
precipitation of Zn.sub.2Mg (.eta.') and Al.sub.2CuMg (S')
phases.
[0024] The alloys of this invention contain aluminum solid
solutions containing at least one element selected from zinc,
copper and magnesium. These alloys also contain precipitates
consisting of fine dispersions of Zn.sub.2Mg (.zeta.') and
Al.sub.2CuMg (S') phases by decomposition of supersaturated solid
solutions. In the solid solutions are dispersions of Al.sub.3X
having an L1.sub.2 structure where X is at least one element
selected from scandium, erbium, thulium, ytterbium, and lutetium
and at least one element selected from gadolinium, yttrium,
zirconium, titanium, hafnium, and niobium.
[0025] Exemplary aluminum alloys of this invention include, but are
not limited to (in weight percent):
[0026] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.1-4.0)Gd;
[0027] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-6)Er-(0.1-4.0)Gd;
[0028] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-10)Tm-(0.1-4.0)Gd;
[0029] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-15)Yb-(0.1-4.0)Gd;
[0030] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-12)Lu-(0.1-4.0)Gd;
[0031] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.1-4.0)Y;
[0032] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-6)Er-(0.1-4.0)Y;
[0033] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-10)-Tm-(0.1-4.0)Y;
[0034] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-15)Yb-(0.1-4.0)Y;
[0035] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-12)Lu-(0.1-4.0)Y;
[0036] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-1.0)Zr;
[0037] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-6)Er-(0.05-1.0)Zr;
[0038] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-1.0)Zr;
[0039] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-1.0)Zr;
[0040] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-12)Lu-(0.05-1.0)Zr;
[0041] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-2.0)Ti;
[0042] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-6)Er-(0.05-2.0)Ti;
[0043] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-2.0)Ti;
[0044] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-2.0)Ti;
[0045] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-12)Lu-(0.05-2.0)Ti;
[0046] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-2.0)Hf;
[0047] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-6)Er-(0.05-2.0)Hf;
[0048] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-2.0)Hf;
[0049] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-2.0)Hf;
[0050] about Al-(3-12)Zn-(0.5-3.5)Mg-((0.1-12)Lu-(0.05-2.0)Hf;
[0051] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-1.0)Nb;
[0052] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-6)Er-(0.05-1.0)Nb;
[0053] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-1.0)Nb;
[0054] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-1.0)Nb;
[0055] about Al-(3-12)Zn-(0.5-3.5)Mg-(0.1-12)Lu-(0.05-1.0)Nb;
[0056] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.1-4.0)Gd;
[0057] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-6)Er-(0.1-4.0)Gd;
[0058] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-10)Tm-(0.1-4.0)Gd;
[0059] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-15)Yb-(0.1-4.0)Gd;
[0060] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-12)Lu-(0.1-4.0)Gd;
[0061] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.1-4.0)Y;
[0062] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-6)Er-(0.1-4.0)Y;
[0063] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-10)-Tm-(0.1-4.0)Y;
[0064] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-15)Yb-(0.1-4.0)Y;
[0065] about
Al-(3-12)Zn-(0.2-3)Cu-(0.5-3.5)Mg-(0.1-12)Lu-(0.1-4.0)Y;
[0066] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-1.0)Zr;
[0067] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-6)Er-(0.05-1.0)Zr;
[0068] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-1.0)Zr;
[0069] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-1.0)Zr;
[0070] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-12)Lu-(0.05-1.0)Zr;
[0071] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-2.0)Ti;
[0072] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-6)Er-(0.05-2.0)Ti;
[0073] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-2.0)Ti;
[0074] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-2.0)Ti;
[0075] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-12)-Lu-(0.05-2.0)Ti;
[0076] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-2.0)Hf;
[0077] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-6)Er-(0.05-2.0)Hf;
[0078] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-2.0)Hf;
[0079] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-2.0)Hf;
[0080] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-12)Lu-(0.05-2.0)Hf;
[0081] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-0.5)Sc-(0.05-1.0)Nb;
[0082] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-6)Er-(0.05-1.0)Nb;
[0083] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-10)Tm-(0.05-1.0)Nb;
[0084] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-15)Yb-(0.05-1.0)Nb; and
[0085] about Al-(3-12)Zn-(0.2-3)Cu
-(0.5-3.5)Mg-(0.1-12)Lu-(0.05-1.0)Nb.
[0086] 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.
[0087] 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 840.degree. F.
(450.degree. C.). 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.
[0088] 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.
Additions of zinc and copper in aluminum provide significant
precipitation strengthening through precipitation of fine second
phases Zn.sub.2Mg (.eta.') and Al.sub.2CuMg (S'). 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.
[0089] 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 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. Additions of zinc and copper in aluminum provide
significant precipitation strengthening through precipitation of
fine second phases Zn.sub.2Mg (.eta.') and Al.sub.2CuMg (S'). 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.
[0090] 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.
Additions of zinc and copper in aluminum provide significant
precipitation strengthening through precipitation of fine second
phases Zn.sub.2Mg (.eta.') and Al.sub.2CuMg (S'). 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.
[0091] 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.
Additions of zinc and copper in aluminum provide significant
precipitation strengthening through precipitation of fine second
phases Zn.sub.2Mg (.eta.') and Al.sub.2CuMg (S'). 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.
[0092] Gadolinium forms metastable Al.sub.3Gd dispersoids in the
aluminum matrix that 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.
[0093] 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.9 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.
[0094] 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.
[0095] 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.
[0096] 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.
[0097] 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.
[0098] 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.
[0099] The alloys are based on aluminum zinc copper magnesium
systems. 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 L1.sub.2 Al.sub.3X phases where X
is at least one element selected from scandium, erbium, thulium,
ytterbium, and lutetium and at least on element selected from
gadolinium, yttrium, zirconium, titanium, hafnium, and niobium.
Additions of zinc and copper in aluminum provide significant
precipitation strengthening through precipitation of fine second
phases Zn.sub.2Mg (.eta.') and Al.sub.2CuMg (S'). The amount of
zinc in these alloys ranges from about 3.0 to about 12.0 weight
percent, more preferably about 4.0 to about 10.0 weight percent,
and even more preferably about 5.0 to about 9.0 weight percent. The
amount of magnesium in these alloys ranges from about 0.5 to about
3.5 weight percent, more preferably about 1.0 to about 3.0 weight
percent, and even more preferably about 1.5 to about 3.0 weight
percent. The amount of copper in these alloys ranges from about 0.2
to about 3.0 weight percent, more preferably about 0.5 to about 2.5
weight percent, and even more preferably about 1.0 to about 2.5
weight percent.
[0100] 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. 4 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.
Alloys with scandium in excess of the eutectic composition cooled
normally will have a microstructure consisting of relatively large
Al.sub.3Sc grains in a finally divided aluminum-Al.sub.3Sc eutectic
phase matrix.
[0101] 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 4.0 weight
percent, and even more preferably from about 0.2 to about 2.0
weight percent. The Al--Er phase diagram shown in FIG. 5 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 dispersoids in a finely
divided aluminum-Al.sub.3Er eutectic phase matrix.
[0102] The amount of thulium present in the alloys of this
invention, if any, may vary from about 0.1 to about 10.0 weight
percent, more preferably from about 0.2 to about 6.0 weight
percent, and even more preferably from about 0.2 to about 4.0
weight percent. The Al--Tm phase diagram shown in FIG. 6 indicates
a eutectic reaction at about 10 weight percent thulium at about
1193.degree. F. (645.degree. C.). Thulium forms metastable
Al.sub.3.TM. dispersoids in the aluminum matrix that have an
L1.sub.2 structure in the equilibrium condition. The Al.sub.3.TM.
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.3.TM. 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.
[0103] The amount of ytterbium present in the alloys of this
invention, if any, may vary from about 0.1 to about 15.0 weight
percent, more preferably from about 0.2 to about 8.0 weight
percent, and even more preferably from about 0.2 to about 4.0
weight percent. The Al--Yb phase diagram shown in FIG. 7 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. Alloys with ytterbium in
excess of the eutectic composition cooled normally will have a
microstructure consisting of relatively large Al.sub.3Yb grains in
a finally divided aluminum-Al.sub.3Yb eutectic phase matrix.
[0104] The amount of lutetium present in the alloys of this
invention, if any, may vary from about 0.1 to about 12.0 weight
percent, more preferably from about 0.2 to about 8.0 weight
percent, and even more preferably from about 0.2 to about 4.0
weight percent. The Al--Lu phase diagram shown in FIG. 8 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. Alloys with lutetium in excess of the eutectic
composition cooled normally will have a microstructure consisting
of relatively large Al.sub.3Lu grains in a finely divided
aluminum-Al.sub.3Lu eutectic phase matrix.
[0105] 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.
[0106] 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.
[0107] 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.
[0108] The amount of titanium 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.
[0109] 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.
[0110] 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.
[0111] 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, about 0.1 weight percent
chromium, about 0.1 weight percent manganese, about 0.1 weight
percent vanadium, about 0.1 weight percent cobalt, and about 0.1
weight percent nickel. The total quantity of additional elements
should not exceed about 1% by weight, including the above listed
impurities and other elements.
[0112] Other additions in the alloys of this invention 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
calcium, about 0.001 weight percent to about 0.10 weight percent
strontium, about 0.001 weight percent to about 0.10 weight percent
antimony, about 0.001 weight percent to about 0.10 weight percent
barium and about 0.001 weight percent to about 0.10 weight percent
phosphorus. These are added to refine the microstructure of the
eutectic phase and the primary magnesium or lithium morphology and
size.
[0113] 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 that about 1. .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.
[0114] More preferred examples of similar alloys to these are
alloys with about 1.0 to about 3.0 weight percent magnesium, alloys
with about 4.0 to about 10.0 weight percent zinc, and alloys with
about 0.5 to about 2.5 weight percent copper, and include, but are
not limited to (in weight percent):
[0115] about Al-(4-10)Zn-(1-3)Mg-(0.1-0.35)Sc-(0.2-2.0)Gd;
[0116] about Al-(4-10)Zn-(1-3)Mg-(0.1-4)Er-(0.2-2.0)Gd;
[0117] about Al-(4-10)Zn-(1-3)Mg-(0.2-6)Tm-(0.2-2.0)Gd;
[0118] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Yb-(0.2-2.0)Gd;
[0119] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Lu-(0.2-2.0)Gd;
[0120] about Al-(4-10)Zn-(1-3)Mg-(0.1-0.35)Sc-(0.2-2.0)Y;
[0121] about Al-(4-10)Zn-(1-3)Mg-(0.1-4)Er-(0.2-2.0)Y;
[0122] about Al-(4-10)Zn-(1-3)Mg-(0.2-6)Tm-(0.2-2.0)Y;
[0123] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Yb-(0.2-2.0)Y;
[0124] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Lu-(0.2-2.0)Y;
[0125] about Al-(4-10)Zn-(1-3)Mg-(0.1-0.35)Sc-(0.1-0.75)Zr;
[0126] about Al-(4-10)Zn-(1-3)Mg-(0.1-4)Er-(0.1-0.75)Zr;
[0127] about Al-(4-10)Zn-(1-3)Mg-(0.2-6)Tm-(0.1-0.75)Zr;
[0128] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Yb-(0.1-0.75)Zr;
[0129] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Lu-(0.1-0.75)Zr;
[0130] about Al-(4-10)Zn-(1-3)Mg-(0.1-0.35)Sc-(0.1-1.0)Ti;
[0131] about Al-(4-10)Zn-(1-3)Mg-(0.1-4)Er-(0.1-1.0)Ti;
[0132] about Al-(4-10)Zn-(1-3)Mg-(0.2-6)Tm-(0.1-1.0)Ti;
[0133] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Yb-(0.1-1.0)Ti;
[0134] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Lu-(0.1-1.0)Ti;
[0135] about Al-(4-10)Zn-(1-3)Mg-(0.1-0.35)Sc-(0.1-1.0)Hf;
[0136] about Al-(4-10)Zn-(1-3)Mg-(0.1-4)Er-(0.1-1.0)Hf;
[0137] about Al-(4-10)Zn-(1-3)Mg-(0.2-6)Tb-(0.1-1.0)Hf;
[0138] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Yb-(0.1-1.0)Hf;
[0139] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Lu-(0.1-1.0)Hf;
[0140] about Al-(4-10)Zn-(1-3)Mg-(0.1-0.35)Sc-(0.1-0.75)Nb;
[0141] about Al-(4-10)Zn-(1-3)Mg-(0.1-4)Er-(0.1-0.75)Nb;
[0142] about Al-(4-10)Zn-(1-3)Mg-(0.2-6)Tm-(0.1-0.75)Nb;
[0143] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Yb-(0.1-0.75)Nb;
[0144] about Al-(4-10)Zn-(1-3)Mg-(0.2-8)Lu-(0.1-0.75)Nb;
[0145] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-0.35)Sc-(0.2-2.0)Gd;
[0146] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-4)Er-(0.2-2.0)Gd;
[0147] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-6)Tm-(0.2-2.0)Gd;
[0148] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Yb-(0.2-2.0)Gd;
[0149] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Lu-(0.2-2.0)Gd;
[0150] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-0.35)Sc-(0.2-2.0)Y;
[0151] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-4)Er-(0.2-2.0)Y;
[0152] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-6)-Tm-(0.2-2.0)Y;
[0153] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Yb-(0.2-2.0)Y;
[0154] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Lu-(0.2-2.0)Y;
[0155] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-0.35)Sc-(0.1-0.75)Zr;
[0156] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-4)Er-(0.1-0.75)Zr;
[0157] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-6)Tm-(0.1-0.75)Zr;
[0158] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Yb-(0.1-0.75)Zr;
[0159] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Lu-(0.1-0.75)Zr;
[0160] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-0.35)Sc-(0.1-1.0)Ti;
[0161] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-4)Er-(0.1-1.0)Ti;
[0162] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-6)Tm-(0.1-1.0)Ti;
[0163] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Yb-(0.1-1.0)Ti;
[0164] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Lu-(0.1-1.0)Ti;
[0165] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-0.35)Sc-(0.1-1.0)Hf;
[0166] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-4)Er-(0.1-1.0)Hf;
[0167] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-6)Tb-(0.1-1.0)Hf;
[0168] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Yb-(0.1-1.0)Hf;
[0169] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Lu-(0.1-1.0)Hf;
[0170] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-0.35)Sc-(0.1-0.75)Nb;
[0171] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.1-4)Er-(0.1-0.75)Nb;
[0172] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-6)Tm-(0.1-0.75)Nb;
[0173] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Yb-(0.1-0.75)Nb; and
[0174] about
Al-(4-10)Zn-(0.5-2.5)Cu-(1-3)Mg-(0.2-8)Lu-(0.1-0.75)Nb.
[0175] Even more preferred examples of similar alloys to these are
alloys with about 1.5 to about 3.0 weight percent magnesium, alloys
with about 5.0 to about 9.0 weight percent zinc, and alloys with
about 1.0 to about 2.5 weight percent copper, and include, but are
not limited to (in weight percent):
[0176] about Al-(5-9)Zn-(1.5-3)Mg-(0.1-0.25)Sc-(0.5-2.0)Gd;
[0177] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-2)Er-(0.5-2.0)Gd;
[0178] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Tm-(0.5-2.0)Gd;
[0179] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Yb-(0.5-2.0)Gd;
[0180] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Lu-(0.5-2.0)Gd;
[0181] about Al-(5-9)Zn-(1.5-3)Mg-(0.1-0.25)Sc-(0.5-2.0)Y;
[0182] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-2)Er-(0.5-2.0)Y;
[0183] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Tm-(0.5-2.0)Y;
[0184] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Yb-(0.5-2.0)Y;
[0185] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Lu-(0.5-2.0)Y;
[0186] about Al-(5-9)Zn-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Zr;
[0187] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Zr;
[0188] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Zr;
[0189] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Zr;
[0190] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Lu-(0.1-0.5)Zr;
[0191] about Al-(5-9)Zn-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Ti;
[0192] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Ti;
[0193] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Ti;
[0194] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Ti;
[0195] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)-Lu-(0.1-0.5)Ti;
[0196] about Al-(5-9)Zn-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Hf;
[0197] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Hf;
[0198] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Hf;
[0199] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Hf;
[0200] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Lu-(0.1-0.5)Hf;
[0201] about Al-(5-9)Zn-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Nb;
[0202] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Nb;
[0203] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Nb;
[0204] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Nb;
[0205] about Al-(5-9)Zn-(1.5-3)Mg-(0.2-4)Lu-(0.1-0.5)Nb;
[0206] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.1-0.25)Sc-(0.2-2.0)Gd;
[0207] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-2)Er-(0.2-2.0)Gd;
[0208] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Tm-(0.2-2.0)Gd;
[0209] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Yb-(0.2-2.0)Gd;
[0210] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Lu-(0.2-2.0)Gd;
[0211] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.1-0.25)Sc-(0.5-2.0)Y;
[0212] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-2)Er-(0.5-2.0)Y;
[0213] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Tm-(0.5-2.0)Y;
[0214] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Yb-(0.5-2.0)Y;
[0215] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Lu-(0.5-2.0)Y;
[0216] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Zr;
[0217] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Zr;
[0218] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Zr;
[0219] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Zr;
[0220] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Lu-(0.1-0.5)Zr;
[0221] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Ti;
[0222] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Ti;
[0223] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Ti;
[0224] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Ti;
[0225] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Lu-(0.1-0.5)Ti;
[0226] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Hf;
[0227] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Hf;
[0228] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Hf;
[0229] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Hf;
[0230] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Lu-(0.1-0.5)Hf;
[0231] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.1-0.25)Sc-(0.1-0.5)Nb;
[0232] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-2)Er-(0.1-0.5)Nb;
[0233] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Tm-(0.1-0.5)Nb;
[0234] about Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Yb-(0.1-0.5)Nb;
and
[0235] about
Al-(5-9)Zn-(1-2.5)Cu-(1.5-3)Mg-(0.2-4)Lu-(0.1-0.5)Nb.
[0236] 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.
* * * * *