[0001] The present invention relates generally to aluminum alloys and more specifically
to heat treatable aluminum alloys produced by melt processing and strengthened by
L1
2 phase dispersions.
[0002] 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°F (149°C)
since most aluminum alloys start to lose strength in that temperature range as a result
of coarsening of strengthening precipitates.
[0003] 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.
[0004] 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.
[0005] U.S. Patent No. 6,248,453 discloses aluminum alloys strengthened by dispersed Al
3X L1
2 intermetallic phases where X is selected from the group consisting of Sc, Er, Lu,
Yb, Tm, and U. The Al
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
2 aluminum alloys are stable up to 572°F (300°C). In order to create aluminum alloys
containing fine dispersions of Al
3X L1
2 particles, the alloys need to be manufactured by expensive rapid solidification processes
with cooling rates in excess of 1.8x10
3°F/sec (10
3°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.
[0006] Heat treatable aluminum alloys strengthened by coherent L1
2 intermetallic phases produced by standard, inexpensive melt processing techniques
would be useful.
[0007] JP 09104940 discloses an Al-Cu base alloy with various additions including scandium and zirconium.
[0009] Cabibbo M et al: "A TEM study of the combined effect of severe plastic deformation
and (Zr), (Sc + Zr) - containing dispersoids on an Al-Mg-Si alloy",
US 2005/013725 and Litynska- Dobrzynska, L: "Effect of heat treatment on the sequence of phases
formation in Al-Mg-Si alloy with Sc and Zr additions" all disclose Al-My-Si alloys
with at least one of scandium or zircondium addition.
[0010] 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°F (343°C).
[0011] These alloys comprise silicon, magnesium, and an Al
3X L1
2 dispersoid where X is at least one first element selected from erbium, thulium, ytterbium,
and lutetium, and at least one second element selected from gadolinium, yttrium, titanium,
hafnium, and niobium. The balance is substantially aluminum.
[0012] The alloys may also have less than 1.0 weight percent total impurities.
[0013] The present invention provides a heat treatable aluminum alloy consisting of: 0.2
to 3.0 weight percent magnesium; at least one element selected from the group consisting
of 0.1 to 2.0 weight percent silicon, and 0.1 to 2.0 weight percent manganese; at
least one first element selected from the group consisting of 0.1 to 6.0 weight percent
erbium, 0.1 to 10 weight percent thulium, 0.1 to 15.0 weight percent ytterbium, and
0.1 to 12 weight percent lutetium; at least one second element selected from the group
consisting of 0.1 to 4.0 weight percent gadolinium, 0.1 to 4.0 weight percent yttrium,
0.05 to 2.0 weight percent titanium, 0.05 to 2.0 weight percent hafnium, and 0.05
to 1.0 weight percent niobium; optionally consisting of at least one of 0.001 to 0.1
weight percent sodium, 0.001 to 0.1 weight percent calcium, 0.001 to 0.1 weight percent
strontium, 0.001 to 0.1 weight percent antimony, 0.001 to 0.1 weight percent barium,
and 0.001 to 0.1 weight percent phosphorus, consisting of no more than 1.0 weight
percent total other elements including impurities, and; optionally consisting of no
more than 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; and the balance
being aluminum with unavoidable impurities.
[0014] In another aspect the present invention provides a method of forming a heat treatable
aluminum alloy, the method comprising: (a) forming a melt consisting of: 0.2 to 3.0
weight percent magnesium; at least one element selected from the group consisting
of 0.1 to 2.0 weight percent silicon, and 0.1 to 2.0 weight percent manganese; at
least one first element selected from the group consisting of 0.1 to 6.0 weight percent
erbium, 0.1 to 10 weight percent thulium, 0.1 to 15.0 weight percent ytterbium, and
0.1 to 12 weight percent lutetium; at least one second element selected from the group
consisting of 0.1 to 4.0 weight percent gadolinium, 0.1 to 4.0 weight percent yttrium,
0.05 to 2.0 weight percent titanium, 0.05 to 2.0 weight percent hafnium, and 0.05
to 1.0 weight percent niobium; optionally consisting of at least one of 0.001 to 0.1
weight percent sodium, 0.001 to 0.1 weight percent calcium, 0.001 to 0.1 weight percent
strontium, 0.001 to 0.1 weight percent antimony, 0.001 to 0.1 weight percent barium,
and 0.001 to 0.1 weight percent phosphorus, consisting of no more than 1.0 weight
percent total other elements including impurities, and; optionally consisting of no
more than 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; and the balance
being aluminum with unavoidable impurities; (b) solidifying the melt to form a solid
body; and (c) heat treating the solid body.
[0015] 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°F (426°C) to about 1100°F (593°C) for between about 30 minutes and four
hours, followed by quenching in water, and thereafter aged at a temperature from about
200°F (93°C) to about 600°F (315°C) for about two to forty eight hours.
[0016] Certain preferred embodiments of the invention will now be described by way of example
only and with reference to the accompanying drawings.
FIG. 1 is an aluminum silicon phase diagram.
FIG. 2 is an aluminum magnesium phase diagram.
FIG. 3 is an aluminum manganese phase diagram.
FIG. 4 is an aluminum erbium phase diagram.
FIG. 5 is an aluminum thulium phase diagram.
FIG. 6 is an aluminum ytterbium phase diagram.
FIG. 7 is an aluminum lutetium phase diagram
[0017] The alloys of this invention are based on the aluminum-magnesium-silicon system.
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°F (577°C). There is little solubility of silicon in aluminum at temperatures
up to 930°F (500°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.
[0018] 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 from about 800°F (425°C) to about 1100°F (593°C) for between about
30 minutes and four hours, followed by quenching in a liquid, and thereafter aged
at a temperature from about 200°F (93°C) to about 600°F (315°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°F (450°C). Magnesium has maximum solid solubility of 16 weight percent in
aluminum at 842°F (450°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.
[0019] The aluminum manganese phase diagram is shown in FIG. 3. The aluminum manganese binary
system is a eutectic alloy system with a eutectic reaction at 2.0 weight percent manganese
and 1216.4°F (658°C). Manganese has maximum solid solubility of about 2 weight percent
in aluminum at 1216.4°F (658°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
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.
[0020] Aluminum-magnesium-silicon alloys can include manganese. Mg
2Si and Si crystals precipitate in aluminum-magnesium-silicon alloys following a solution
heat treatment, quench, and age process. Mg
2Al
3 (β) 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
2 phase prevents formation of β phase in this material which improves ductility and
toughness of material. In the solid solutions of the alloys of this invention are
dispersions of Al
3X having an L1
2 structure where X is at least one first element selected from erbium, thulium, ytterbium,
and lutetium. Also present is at least one second element selected from gadolinium,
yttrium, titanium, hafnium, and niobium.
[0021] Exemplary aluminum alloys of this invention include, but are not limited to (in weight
percent):
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-0.1-6)Er-(0.1-4)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.1-4)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.1-4)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.1-4)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.1-4)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.1-4)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.1-4)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.1-4)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.05-2)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-2)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-2)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-2)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.05-2)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-2)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-2)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-2)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-6)Er-(0.05-1)Nb;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-10)Tm-(0.05-1)Nb;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-15)Yb-(0.05-1)Nb; and
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-12)Lu-(0.05-1)Nb.
[0022] 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.
[0023] In the inventive aluminum based alloys disclosed herein, erbium, thulium, ytterbium,
and lutetium are potent strengtheners that have low diffusivity and low solubility
in aluminum. All these elements form equilibrium Al
3X intermetallic dispersoids where X is at least one of erbium, ytterbium, lutetium,
that have an L1
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.
[0024] Erbium forms Al
3Er dispersoids in the aluminum matrix that are fine and coherent with the aluminum
matrix. The lattice parameters of aluminum and Al
3Er are close (0.405 nm and 0.417 nm respectively), indicating there is minimal driving
force for causing growth of the Al
3Er dispersoids. This low interfacial energy makes the Al
3Er dispersoids thermally stable and resistant to coarsening up to temperatures as
high as about 842°F (450°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
3Er to coarsening. In the alloys of this invention, these Al
3Er dispersoids are made stronger and more resistant to coarsening at elevated temperatures
by adding suitable alloying elements such as gadolinium, yttrium, titanium, hafnium,
niobium, or combinations thereof that enter Al
3Er in solution.
[0025] Thulium forms metastable Al
3Tm dispersoids in the aluminum matrix that are fine and coherent with the aluminum
matrix. The lattice parameters of aluminum and Al
3Tm are close (0.405 nm and 0.420 nm respectively), indicating there is minimal driving
force for causing growth of the Al
3Tm dispersoids. This low interfacial energy makes the Al
3Tm dispersoids thermally stable and resistant to coarsening up to temperatures as
high as about 842°F (450°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. In the alloys of
this invention these Al
3Tm dispersoids are made stronger and more resistant to coarsening at elevated temperatures
by adding suitable alloying elements such as gadolinium, yttrium, titanium, hafnium,
niobium, or combinations thereof that enter Al
3Tm in solution.
[0026] Ytterbium forms Al
3Yb dispersoids in the aluminum matrix that are fine and coherent with the aluminum
matrix. The lattice parameters of Al and Al
3Yb are close (0.405 nm and 0.420 nm respectively), indicating there is minimal driving
force for causing growth of the Al
3Yb dispersoids. This low interfacial energy makes the Al
3Yb dispersoids thermally stable and resistant to coarsening up to temperatures as
high as about 842°F (450°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
3Yb. In the alloys of this invention, these Al
3Yb dispersoids are made stronger and more resistant to coarsening at elevated temperatures
by adding suitable alloying elements such as gadolinium, yttrium, titanium, hafnium,
niobium, or combinations thereof that enter Al
3Yb in solution.
[0027] Lutetium forms Al
3Lu dispersoids in the aluminum matrix that are fine and coherent with the aluminum
matrix. The lattice parameters of Al and Al
3Lu are close (0.405 nm and 0.419 nm respectively), indicating there is minimal driving
force for causing growth of the Al
3Lu dispersoids. This low interfacial energy makes the Al
3Lu dispersoids thermally stable and resistant to coarsening up to temperatures as
high as about 842°F (450°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
3Lu. In the alloys of this invention, these Al
3Lu dispersoids are made stronger and more resistant to coarsening at elevated temperatures
by adding suitable alloying elements such as gadolinium, yttrium, titanium, hafnium,
niobium, or mixtures thereof that enter Al
3Lu in solution.
[0028] Gadolinium forms metastable Al
3Gd dispersoids in the aluminum matrix that have an L1
2 structure in the metastable condition. The Al
3Gd dispersoids are stable up to temperatures as high as about 842°F (450°C) due to
their low diffusivity in aluminum. The Al
3Gd dispersoids have a D0
19 structure in the equilibrium condition. Despite its large atomic size, gadolinium
has fairly high solubility in the Al
3X intermetallic dispersoids (where X is erbium, thulium, ytterbium or lutetium). Gadolinium
can substitute for the X atoms in Al
3X intermetallic, thereby forming an ordered L1
2 phase which results in improved thermal and structural stability.
[0029] Yttrium forms metastable Al
3Y dispersoids in the aluminum matrix that have an L1
2 structure in the metastable condition and a D0
19 structure in the equilibrium condition. The metastable Al
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
3X intermetallic dispersoids allowing large amounts of yttrium to substitute for X
in the Al
3X L1
2 dispersoids which results in improved thermal and structural stability.
[0030] Titanium forms Al
3Ti dispersoids in the aluminum matrix that have an L1
2 structure in the metastable condition and D0
22 structure in the equilibrium condition. The metastable Al
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
3X dispersoids allowing large amounts of titanium to substitute for X in the Al
3X dispersoids, which results in improved thermal and structural stability.
[0031] Hafnium forms metastable Al
3Hf dispersoids in the aluminum matrix that have an L1
2 structure in the metastable condition and a D0
23 structure in the equilibrium condition. The Al
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
3X dispersoids allowing large amounts of hafnium to substitute for erbium, thulium,
ytterbium, and lutetium in the above mentioned Al
3X dispersoids, which results in stronger and more thermally stable dispersoids.
[0032] Niobium forms metastable Al
3Nb dispersoids in the aluminum matrix that have an L1
2 structure in the metastable condition and a D0
22 structure in the equilibrium condition. Niobium has a lower solubility in the Al
3X dispersoids than hafnium or yttrium, allowing relatively lower amounts of niobium
than hafnium or yttrium to substitute for X in the Al
3X dispersoids. Nonetheless, niobium can be very effective in slowing down the coarsening
kinetics of the Al
3X dispersoids because the Al
3Nb dispersoids are thermally stable. The substitution of niobium for X in the above
mentioned Al
3X dispersoids results in stronger and more thermally stable dispersoids.
[0033] Al
3X L1
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
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.
[0034] 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. 4 indicates a eutectic reaction at about 6 weight percent erbium
at about 1211°F (655°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
2 intermetallic Al
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
3°C/second. Alloys with erbium in excess of the eutectic composition (hypereutectic
alloys) cooled normally will have a microstructure consisting of relatively large
Al
3Er dispersoid in a finely divided aluminum-Al
3Er eutectic phase matrix.
[0035] 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. 5 indicates a eutectic reaction at about 10 weight percent
thulium at about 1193°F (645°C). Thulium forms metastable Al
3Tm dispersoids in the aluminum matrix that have an L1
2 structure in the equilibrium condition. The Al
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
2 intermetallic Al
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
3°C/second.
[0036] 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. 6 indicates a eutectic reaction at about 21
weight percent ytterbium at about 1157°F (625°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
2 intermetallic Al
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
3°C/second.
[0037] 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. 7 indicates a eutectic reaction at about 11.7 weight percent
Lu at about 1202°F (650°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
2 intermetallic Al
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
3°C/second.
[0038] 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.
[0039] 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.
[0040] 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.
[0041] 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.
[0042] 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.
[0043] 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.
[0044] 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.
[0045] 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
3°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.
[0046] Preferred exemplary aluminum alloys of this invention include, but are not limited
to (in weight percent):
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-4)Er-(0.2-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.2-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.2-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.2-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.1-4)Er-(0.2-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.2-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.2-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.2-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg(0.1-4)Er-(0.1-1)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-1)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-1)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-1)Ti;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg(0.1-4)Er-(0.1-1)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-1)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-1)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-1)Hf;
about Al-(0.1-2.0)Si -(0.2-3.0)Mg -(0.2-2)Er-(0.1-0.75)Nb;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-6)Tm-(0.1-0.75)Nb;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Yb-(0.1-0.75)Nb; and
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-8)Lu-(0.1-0.75)Nb.
[0047] 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.
[0048] Even more preferred exemplary aluminum alloys of this invention include, but are
not limited to (in weight percent):
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.5-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.5-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.5-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.5-2)Gd;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.5-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.5-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.5-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.5-2)Y;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Zr;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(02-4)Tm-(0.1-0.5)Zr;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Zr;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Zr;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Hf;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-2)Er-(0.1-0.5)Nb;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Tm-(0.1-0.5)Nb;
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Yb-(0.1-0.5)Nb; and
about Al-(0.1-2.0)Si-(0.2-3.0)Mg-(0.2-4)Lu-(0.1-0.5)Nb.
[0049] 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.
[0050] 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 scope of the invention as defined by the attached claims.
[0051] One aspect of at least the preferred embodiment of the present invention is 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, and about 0.1 to about 2.0 weight percent manganese; an aluminum
solid solution matrix containing a plurality of dispersed Al
3X second phases having L1
2 structures where X comprises at least one of erbium, thulium, ytterbium, lutetium,
and at least one of gadolinium, yttrium, titanium, hafnium, niobium.
[0052] Preferably wherein the alloy comprises an aluminum solid solution matrix, precipitates
including but not limited to Mg
2Si, Al
6Mn, and a plurality of dispersed Al
3X second phases having L1
2 structures where X comprises at least one of erbium, thulium, ytterbium, lutetium,
and at least one of gadolinium, yttrium, titanium, hafnium, niobium.
[0053] Preferably wherein the alloy comprises at least one of 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.
1. A heat treatable aluminum alloy consisting of:
0.2 to 3.0 weight percent magnesium;
at least one element selected from the group consisting of 0.1 to 2.0 weight percent
silicon, and 0.1 to 2.0 weight percent manganese;
at least one first element selected from the group consisting of 0.1 to 6.0 weight
percent erbium, 0.1 to 10 weight percent thulium, 0.1 to 15.0 weight percent ytterbium,
and 0.1 to 12 weight percent lutetium;
at least one second element selected from the group consisting of 0.1 to 4.0 weight
percent gadolinium, 0.1 to 4.0 weight percent yttrium, 0.05 to 2.0 weight percent
titanium, 0.05 to 2.0 weight percent hafnium, and 0.05 to 1.0 weight percent niobium;
optionally consisting of at least one of 0.001 to 0.1 weight percent sodium, 0.001
to 0.1 weight percent calcium, 0.001 to 0.1 weight percent strontium, 0.001 to 0.1
weight percent antimony, 0.001 to 0.1 weight percent barium, and 0.001 to 0.1 weight
percent phosphorus,
consisting of no more than 1.0 weight percent total other elements including impurities,
and;
optionally consisting of no more than 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; and
the balance being aluminum with unavoidable impurities.
2. The alloy of claim 1, wherein the alloy comprises an aluminum solid solution matrix
containing a plurality of dispersed Al3X second phases having L12 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 Mg2Si, and Al6Mn;
a plurality of dispersed Al3X second phases having L12 structures, wherein X includes at least one first element selected from the group
consisting of 0.1 to 6.0 weight percent erbium, 0.1 to 10 weight percent thulium,
0.1 to 15.0 weight percent ytterbium, and 0.1 to 12 weight percent lutetium; and
at least one second element selected from the group consisting of 0.1 to 4.0 weight
percent gadolinium, 0.1 to 4.0 weight percent yttrium, 0.05 to 2.0 weight percent
titanium, 0.05 to 2.0 weight percent hafnium, and 0.05 to 1.0 weight percent niobium;
and
the balance being aluminum with unavoidable impurities.
4. The alloy of claim 1, 2 or 3, wherein the at least one element selected from the group
consisting of 0.1 to 2.0 weight percent silicon, 0.2 to 6.5 weight percent copper,
0.1 to 2.0 weight percent manganese is 0.1 to 2.0 weight percent silicon.
5. The alloy of any preceding claim, wherein the amount of silicon ranges from 0.2 to
1.6 weight percent.
6. The alloy of claim 1, 2 or 3, wherein the at least one element selected from the group
consisting of 0.1 to 2.0 weight percent silicon, and 0.1 to 2.0 weight percent manganese
is 0.1 to 2.0 weight percent manganese.
7. A method of forming a heat treatable aluminum alloy, the method comprising:
(a) forming a melt consisting of:
0.2 to 3.0 weight percent magnesium;
at least one element selected from the group consisting of 0.1 to 2.0 weight percent
silicon, and 0.1 to 2.0 weight percent manganese;
at least one first element selected from the group consisting of 0.1 to 6.0 weight
percent erbium, 0.1 to 10 weight percent thulium, 0.1 to 15.0 weight percent ytterbium,
and 0.1 to 12 weight percent lutetium;
at least one second element selected from the group consisting of 0.1 to 4.0 weight
percent gadolinium, 0.1 to 4.0 weight percent yttrium, 0.05 to 2.0 weight percent
titanium, 0.05 to 2.0 weight percent hafnium, and 0.05 to 1.0 weight percent niobium;
optionally consisting of at least one of 0.001 to 0.1 weight percent sodium, 0.001
to 0.1 weight percent calcium, 0.001 to 0.1 weight percent strontium, 0.001 to 0.1
weight percent antimony, 0.001 to 0.1 weight percent barium, and 0.001 to 0.1 weight
percent phosphorus,
consisting of no more than 1.0 weight percent total other elements including impurities,
and;
optionally consisting of no more than 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; and
the balance being aluminum with unavoidable impurities.
(b) solidifying the melt to form a solid body; and
(c) heat treating the solid body.
8. The method of claim 7 further comprising:
refining the structure of the solid body by deformation processing including but not
limited to these processes: extrusion, forging and rolling.
9. The method of claim 7 or 8, wherein solidifying comprises a rapid solidification process
in which the cooling rate is greater than 103°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.
10. The method of claim 7, 8 or 9, wherein the heat treating comprises:
solution heat treatment at 800°F (426°C) to 1100°F (593°C) for thirty minutes to four
hours; and
quenching; and
aging at a temperature of 200°F (93°C) to 600°F (315°C) for two to forty eight hours.
11. The method of claim 7 comprising forming the alloy by a process selected from casting,
and subsequent deformation processing, and rapid solidification processing.
1. Hitzebehandelbare Aluminiumlegierung, die aus Folgendem besteht:
0,2 bis 3,0 Gewichtsprozent Magnesium;
mindestens einem Element, ausgewählt aus der Gruppe bestehend aus 0,1 bis 2,0 Gewichtsprozent
Silicium und 0,1 bis 2,0 Gewichtsprozent Mangan;
mindestens einem ersten Element, ausgewählt aus der Gruppe bestehend aus 0,1 bis 6,0
Gewichtsprozent Erbium, 0,1 bis 10 Gewichtsprozent Thulium, 0,1 bis 15,0 Gewichtsprozent
Ytterbium und 0,1 bis 12 Gewichtsprozent Lutetium;
mindestens einem zweiten Element, ausgewählt aus der Gruppe bestehend aus 0,1 bis
4,0 Gewichtsprozent Gadolinium, 0,1 bis 4,0 Gewichtsprozent Yttrium, 0,05 bis 2,0
Gewichtsprozent Titan, 0,05 bis 2,0 Gewichtsprozent Hafnium und 0,05 bis 1,0 Gewichtsprozent
Niob;
wahlweise bestehend aus mindestens einem von 0,001 bis 0,1 Gewichtsprozent Natrium,
0,001 bis 0,1 Gewichtsprozent Calcium, 0,001 bis 0,1 Gewichtsprozent Strontium, 0,001
bis 0,1 Gewichtsprozent Antimon, 0,001 bis 0,1 Gewichtsprozent Barium und 0,001 bis
0,1 Gewichtsprozent Phosphor,
bestehend aus nicht mehr als insgesamt 1,0 Gewichtsprozent von anderen Elementen,
einschließlich Verunreinigungen, und; wahlweise bestehend aus nicht mehr als 0,1 Gewichtsprozent
Eisen, 0,1 Gewichtsprozent Chrom, 0,1 Gewichtsprozent Vanadium, 0,1 Gewichtsprozent
Cobalt und 0,1 Gewichtsprozent Nickel; und
wobei der Rest Aluminium mit unvermeidbaren Verunreinigungen ist.
2. Legierung nach Anspruch 1, wobei die Legierung eine Aluminiumfeststofflösungsmatrix
umfasst, die eine Vielzahl von dispergierten Al3X-Zweitphasen enthält, die L12-Strukturen aufweisen, wobei X mindestens ein erstes Element und mindestens ein zweites
Element beinhaltet.
3. Legierung nach Anspruch 1, wobei die Legierung eine Aluminiumfeststofflösungsmatrix
umfasst und einschließlich unter anderem Mg2Si und Al6Mn ausfällt;
wobei eine Vielzahl von dispergierten Al3X-Zweitphasen L12-Strukturen aufweisen, wobei X mindestens ein erstes Element beinhaltet, ausgewählt
aus der Gruppe bestehend aus 0,1 bis 6,0 Gewichtsprozent Erbium, 0,1 bis 10 Gewichtsprozent
Thulium, 0,1 bis 15,0 Gewichtsprozent Ytterbium und 0,1 bis 12 Gewichtsprozent Lutetium;
und
wobei mindestens ein zweites Element ausgewählt ist aus der Gruppe bestehend aus 0,1
bis 4,0 Gewichtsprozent Gadolinium, 0,1 bis 4,0 Gewichtsprozent Yttrium, 0,05 bis
2,0 Gewichtsprozent Titan, 0,05 bis 2.0 Gewichtsprozent Hafnium und 0,05 bis 1,0 Gewichtsprozent
Niob; und
wobei der Rest Aluminium mit unvermeidbaren Verunreinigungen ist.
4. Legierung nach Anspruch 1, 2 oder 3, wobei das mindestens eine Element, das ausgewählt
ist aus der Gruppe bestehend aus 0,1 bis 2,0 Gewichtsprozent Silicium, 0,2 bis 6,5
Gewichtsprozent Kupfer, 0,1 bis 2,0 Gewichtsprozent Mangan, zu 0,1 bis 2,0 Gewichtsprozent
Silicium ist.
5. Legierung nach einem der vorhergehenden Ansprüche, wobei die Menge von Silicium im
Bereich von 0,1 bis 1,6 Gewichtsprozent liegt.
6. Legierung nach Anspruch 1, 2 oder 3, wobei das mindestens eine Element, das ausgewählt
ist aus der Gruppe bestehend aus 0,1 bis 2,0 Gewichtsprozent Silicium und 0,1 bis
2,0 Gewichtsprozent Mangan, zu 0,1 bis 2,0 Gewichtsprozent Mangan ist.
7. Verfahren zum Bilden einer hitzebehandelbaren Aluminiumlegierung, wobei das Verfahren
Folgendes umfasst:
(a) Bilden einer Schmelze, die aus Folgendem besteht:
0,2 bis 3,0 Gewichtsprozent Magnesium;
mindestens einem Element, ausgewählt aus der Gruppe bestehend aus 0,1 bis 2,0 Gewichtsprozent
Silicium und 0,1 bis 2,0 Gewichtsprozent Mangan;
mindestens einem ersten Element, ausgewählt aus der Gruppe bestehend aus 0,1 bis 6,0
Gewichtsprozent Erbium, 0,1 bis 10 Gewichtsprozent Thulium, 0,1 bis 15,0 Gewichtsprozent
Ytterbium und 0,1 bis 12 Gewichtsprozent Lutetium;
mindestens einem zweiten Element, ausgewählt aus der Gruppe bestehend aus 0,1 bis
4,0 Gewichtsprozent Gadolinium, 0,1 bis 4,0 Gewichtsprozent Yttrium, 0,05 bis 2,0
Gewichtsprozent Titan, 0,05 bis 2,0 Gewichtsprozent Hafnium und 0,05 bis 1,0 Gewichtsprozent
Niob;
wahlweise bestehend aus mindestens einem von 0,001 bis 0,1 Gewichtsprozent Natrium,
0,001 bis 0,1 Gewichtsprozent Calcium, 0,001 bis 0,1 Gewichtsprozent Strontium, 0,001
bis 0,1 Gewichtsprozent Antimon, 0,001 bis 0,1 Gewichtsprozent Barium und 0,001 bis
0,1 Gewichtsprozent Phosphor, bestehend aus nicht mehr als insgesamt 1,0 Gewichtsprozent
von anderen Elementen, einschließlich Verunreinigungen, und;
wahlweise bestehend aus nicht mehr als 0,1 Gewichtsprozent Eisen, 0,1 Gewichtsprozent
Chrom, 0,1 Gewichtsprozent Vanadium, 0,1 Gewichtsprozent Cobalt und 0,1 Gewichtsprozent
Nickel; und
wobei der Rest Aluminium mit unvermeidbaren Verunreinigungen ist.
(b) Verfestigen der Schmelze, um einen Festkörper zu bilden; und
(c) Hitzebehandeln des Festkörpers.
8. Verfahren nach Anspruch 7, das ferner Folgendes umfasst: Verfeinern der Struktur des
Festkörpers durch Verformungsbearbeitung, einschließlich unter anderem dieser Prozesse:
Extrusion, Schmieden und Rollen.
9. Verfahren nach Anspruch 7 oder 8, wobei das Verfestigen einen schnellen Verfestigungsprozess
umfasst, in welchem die Abkühlungsrate größer als 103 °C/Sekunde ist, einschließlich mindestens einem von: Pulververarbeitung, Atomisierung,
Schmelzspinnen, Abschrecken aus der Schmelze, Sprühabscheidung, Kaltsprühen, Plasmasprühen,
Laserschmelzen und -abscheidung, Kugelmahlen und kryogenes Mahlen.
10. Verfahren nach Anspruch 7, 8 oder 9, wobei das Hitzebehandeln Folgendes umfasst:
Hitzebehandlung der Lösung bei 800 °F (426 °C) bis 1100 °F (593 °C) für dreißig Minuten
bis vier Stunden; und Abschrecken; und
Altern bei einer Temperatur von 200 °F (93 °C) bis 600 °F (315 °C) für zwei bis achtundvierzig
Stunden.
11. Verfahren nach Anspruch 7, das Bilden der Legierung durch einen Prozess umfasst, der
ausgewählt ist aus Gießen und nachfolgendem Verformungsverarbeiten und schnellem Verfestigungsverarbeiten.
1. Alliage d'aluminium à traitement thermique composé de :
0,2 à 3,0 pourcent en poids de magnésium ;
au moins un élément choisi dans un groupe composé de 0,1 à 2,0 pourcent en poids de
silicium, et 0,1 à 2,0 pourcent en poids de manganèse ;
au moins un premier élément choisi dans un groupe composé de 0,1 à 6,0 pourcent en
poids d'erbium, 0,1 à 10 pourcent en poids de thulium, 0,1 à 15,0 pourcent en poids
d'ytterbium, et 0,1 à 12 pourcent en poids de lutétium ;
au moins un second élément choisi dans un groupe composé de 0,1 à 4,0 pourcent en
poids de gadolinium, 0,1 à 4,0 pourcent en poids d'yttrium, 0,05 à 2,0 pourcent en
poids de titane, 0,05 à 2,0 pourcent en poids d'hafnium, et 0,05 à 1,0 pourcent en
poids de niobium ;
éventuellement composé d'au moins un de 0,001 à 0,1 pourcent en poids de sodium, 0,001
à 0,1 pourcent en poids de calcium, 0,001 à 0,1 pourcent en poids de strontium, 0,001
à 0,1 pourcent en poids d'antimoine, 0,001 à 0,1 pourcent en poids de baryum, et 0,001
à 0,1 pourcent en poids de phosphore, composé de pas plus de 1,0 pourcent en poids
total d'autres éléments incluant des impuretés, et ;
éventuellement composé de pas plus de 0,1 pourcent en poids de fer, 0,1 pourcent en
poids de chrome, 0,1 pourcent en poids de vanadium, 0,1 pourcent en poids de cobalt,
et 0,1 pourcent en poids de nickel ; et
le reste étant de l'aluminium avec des impuretés inévitables.
2. Alliage selon la revendication 1, dans lequel l'alliage comprend une matrice de solution
solide d'aluminium contenant une pluralité de secondes phases d'Al3X dispersées ayant des structures L12, dans lequel X inclut au moins un premier élément et au moins un second élément.
3. Alliage selon la revendication 1, dans lequel l'alliage comprend une matrice de solution
solide d'aluminium et des précipités incluant mais sans limitation du Mg2Si, et de l'Al6Mn ;
une pluralité de secondes phases d'Al3X dispersées ayant des structures L12, dans lequel X inclut au moins un premier élément choisi dans un groupe composé de
0,1 à 6,0 pourcent en poids d'erbium, 0,1 à 10 pourcent en poids de thulium, 0,1 à
15,0 pourcent en poids d'ytterbium, et 0,1 à 12 pourcent en poids de lutétium ; et
au moins un second élément choisi dans un groupe composé de 0,1 à 4,0 pourcent en
poids de gadolinium, 0,1 à 4,0 pourcent en poids d'yttrium, 0,05 à 2,0 pourcent en
poids de titane, 0,05 à 2,0 pourcent en poids d'hafnium, et 0,05 à 1,0 pourcent en
poids de niobium ; et
le reste étant de l'aluminium avec des impuretés inévitables.
4. Alliage selon la revendication 1, 2 ou 3, dans lequel l'au moins un élément choisi
dans un groupe composé de 0,1 à 2,0 pourcent en poids de silicium, 0,2 à 6,5 pourcent
en poids de cuivre, 0,1 à 2,0 pourcent en poids de manganèse est 0,1 à 2,0 pourcent
en poids de silicium.
5. Alliage selon une quelconque revendication précédente, dans lequel la quantité de
silicium s'inscrit dans la plage de 0,2 à 1,6 pourcent en poids.
6. Alliage selon la revendication 1, 2 ou 3, dans lequel l'au moins un élément choisi
dans un groupe composé de 0,1 à 2,0 pourcent en poids de silicium, et 0,1 à 2,0 pourcent
en poids de manganèse est 0,1 à 2,0 pourcent en poids de manganèse.
7. Procédé de formation d'un alliage d'aluminium à traitement thermique, le procédé comprenant
:
(a) la formation d'une fonte composée de :
0,2 à 3,0 pourcent en poids de magnésium ;
au moins un élément choisi dans un groupe composé de 0,1 à 2,0 pourcent en poids de
silicium, et 0,1 à 2,0 pourcent en poids de manganèse ;
au moins un premier élément choisi dans un groupe composé de 0,1 à 6,0 pourcent en
poids d'erbium, 0,1 à 10 pourcent en poids de thulium, 0,1 à 15,0 pourcent en poids
d'ytterbium, et 0,1 à 12 pourcent en poids de lutétium ;
au moins un second élément choisi dans un groupe composé de 0,1 à 4,0 pourcent en
poids de gadolinium, 0,1 à 4,0 pourcent en poids d'yttrium, 0,05 à 2,0 pourcent en
poids de titane, 0,05 à 2,0 pourcent en poids d'hafnium, et 0,05 à 1,0 pourcent en
poids de niobium ;
éventuellement composé d'au moins 0,001 à 0,1 pourcent en poids de sodium, 0,001 à
0,1 pourcent en poids de calcium, 0,001 à 0,1 pourcent en poids de strontium, 0,001
à 0,1 pourcent en poids d'antimoine, 0,001 à 0,1 pourcent en poids de baryum, et 0,001
à 0,1 pourcent en poids de phosphore, composé de pas plus de 1,0 pourcent en poids
total d'autres éléments incluant des impuretés, et ;
éventuellement composé de pas plus de 0,1 pourcent en poids de fer, 0,1 pourcent en
poids de chrome, 0,1 pourcent en poids de vanadium, 0,1 pourcent en poids de cobalt,
et 0,1 pourcent en poids de nickel ; et
le reste étant de l'aluminium avec des impuretés inévitables ;
(b) la solidification de la fonte pour former un corps solide ; et
(c) le traitement thermique du corps solide.
8. Procédé selon la revendication 7 comprenant en outre :
l'affinement de la structure du corps solide par un processus de déformation incluant
mais sans limitation ces procédés : une extrusion, un forgeage et un laminage.
9. Procédé selon la revendication 7 ou 8, dans lequel la solidification comprend un procédé
de solidification rapide dans lequel la vitesse de refroidissement est supérieure
à 103 °C/seconde incluant au moins un de : un processus de poudre, une atomisation, un
filage par fusion, une hypertrempe, un dépôt par pulvérisation, une projection à froid,
une projection au plasma, une fusion et un dépôt par laser, un broyage à boulets,
et un cryobroyage.
10. Procédé selon la revendication 7, 8 ou 9, dans lequel le traitement thermique comprend
:
un traitement thermique de mise en solution à 800 °F (426 °C) à 1 100 °F (593 °C)
pendant trente minutes à quatre heures ; et
une trempe ; et
un vieillissement à une température de 200 °F (93 °C) à 600 °F (315 °C) pendant deux
à quarante-huit heures.
11. Procédé selon la revendication 7 comprenant la formation de l'alliage par un procédé
choisi parmi un moulage, et un processus de déformation ultérieur, et un processus
de solidification rapide.