Abstract:
An improved amorphous aluminum alloy having high strength, ductility, corrosion resistance and fracture toughness is disclosed. The alloy has an amorphous phase and a coherent L1 2  phase. The alloy has nickel, cerium, at least one of scandium, erbium, thulium, ytterbium, and lutetium; and at least one of gadolinium, yttrium, zirconium, titanium, hafnium, niobium and iron. The volume fraction of the amorphous phase ranges from about 50 percent to about 95 percent and the volume fraction of the coherent L1 2  phase ranges from about 5 percent to about 50 percent.

Description:
CROSS-REFERENCE TO RELATED APPLICATIONS 
     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 2  ALUMINUM ALLOYS WITH BIMODAL AND TRIMODAL DISTRIBUTION, Ser. No. 12/148,395, DISPERSION STRENGTHENED L1 2  ALUMINUM ALLOYS, Ser. No. 12/148,432, HEAT TREATABLE L1 2  ALUMINUM ALLOYS, Ser. No. 12/148,383, HIGH STRENGTH L1 2  ALUMINUM ALLOYS, Ser. No. 12/148,394, HIGH STRENGTH L1 2  ALUMINUM ALLOYS, Ser. No. 12/148,382, HEAT TREATABLE L1 2  ALUMINUM ALLOYS, Ser. No. 12/148,396, HIGH STRENGTH L1 2  ALUMINUM ALLOYS, Ser. No. 12/148,387, HIGH STRENGTH ALUMINUM ALLOYS WITH L1 2  PRECIPITATES, Ser. No. 12/148,426, and HIGH STRENGTH L1 2  ALUMINUM ALLOYS, Ser. No. 12/148,459. 
     BACKGROUND 
     The present invention relates generally to aluminum alloys and more specifically to L1 2  phase dispersion strengthened aluminum alloys having ceramic reinforcement particles. 
     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. 
     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. 
     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. 
     U.S. Pat. No. 6,248,453 discloses aluminum alloys strengthened by dispersed Al 3 X L1 2  intermetallic phases where X is selected from the group consisting of Sc, Er, Lu, Yb, Tm, and U. The Al 3 X 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 F2  aluminum alloys are stable up to 572° F. (300° C.). U.S. Patent Application Publication No. 2006/0269437 A1 discloses an aluminum alloy that contains scandium and other elements. 
     Amorphous alloys have received interest in recent years because materials with an amorphous structure are usually very strong and corrosion resistant in comparison with crystalline structures having the same composition. However, amorphous aluminum alloys have been found to have lower ductility and fracture toughness than the crystalline form. Aluminum based amorphous alloys with high strength and low density are desirable because of their lower density and their applicability in the aerospace and space industries. Amorphous aluminum alloys would also be useful in armor applications where lightweight materials are desired. 
     SUMMARY 
     The present invention is an improved amorphous aluminum alloy having a crystalline L1 2  aluminum alloy phase dispersed in an amorphous aluminum alloy matrix. The L1 2  phase results in improved ductility and fracture toughness while maintaining the strength and corrosion resistance of the amorphous phase. The desired volume fraction of the amorphous phase is from about 50 percent to about 95 percent, more preferably about 60 percent to about 90 percent, and even more preferably about 70 percent to about 80 percent. 
     The aluminum alloy of this invention is formed into the amorphous phase and a fine, coherent L1 2  phase by use of the rapid solidification process. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG. 1  is an aluminum nickel phase diagram. 
         FIG. 2  is an aluminum cerium phase diagram. 
         FIG. 3  is an aluminum scandium 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. 
     
    
    
     DETAILED DESCRIPTION 
     The alloys of this invention comprises an amorphous matrix of aluminum, nickel and cerium strengthened by having dispersed therein a fine, coherent L1 2  phase based on Al 3 X where X is least one first element selected from scandium, erbium, thulium, ytterbium, lutetium, and at least one second element selected from iron, gadolinium, yttrium, zirconium, titanium, hafnium, and niobium. 
     The aluminum nickel phase diagram is shown in  FIG. 1 . The aluminum nickel binary system is a simple eutectic at 5.7 weight percent nickel and 1183.8° F. (639.9° C.). There is little solubility of nickel in aluminum. However, the solubility can be extended significantly by utilizing rapid solidification processes. The equilibrium phase in the aluminum nickel eutectic system is intermetallic Al 3 Ni. 
     The aluminum cerium phase diagram is shown in  FIG. 2 . The aluminum cerium binary system is a simple eutectic at 18 weight percent cerium and 1184° F. (640° C.). There is little or no solubility of cerium in aluminum. However the solubility can be extended significantly by utilizing rapid solidification processes. Metastable Al 3 Ce can form in rapidly cooled hypereutectic aluminum cerium alloys. The equilibrium phase in eutectic alloys is Al 11 Ce 3  Cerium helps in forming an amorphous structure in aluminum in the presence of nickel due to deep eutectics. 
     Scandium forms Al 3 Sc dispersoids that are fine and coherent with the aluminum matrix. Lattice parameters of aluminum and Al 3 Sc 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 3 Sc dispersoids. This low interfacial energy makes the Al 3 Sc dispersoids thermally stable and resistant to coarsening up to temperatures as high as about 842° F. (450° C.). In the alloys of this invention these Al 3 Sc 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, iron or combinations thereof, that enter Al 3 Sc in solution. 
     Erbium forms Al 3 Er dispersoids in the aluminum matrix that are fine and coherent with the aluminum matrix. The lattice parameters of aluminum and Al 3 Er are close (0.405 nm and 0.417 nm respectively), indicating there is minimal driving force for causing growth of the Al 3 Er dispersoids. This low interfacial energy makes the Al 3 Er dispersoids thermally stable and resistant to coarsening up to temperatures as high as about 842° F. (450° C.). In the alloys of this invention, these Al 3 Er 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, iron or combinations thereof that enter Al 3 Er in solution. 
     Thulium forms metastable Al 3 Tm dispersoids in the aluminum matrix that are fine and coherent with the aluminum matrix. The lattice parameters of aluminum and Al 3 Tm are close (0.405 nm and 0.420 nm respectively), indicating there is minimal driving force for causing growth of the Al 3 Tm dispersoids. This low interfacial energy makes the Al 3 Tm dispersoids thermally stable and resistant to coarsening up to temperatures as high as about 842° F. (450° C.). In the alloys of this invention these Al 3 Tm 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, iron or combinations thereof that enter Al 3 Tm in solution. 
     Ytterbium forms Al 3 Yb dispersoids in the aluminum matrix that are fine and coherent with the aluminum matrix. The lattice parameters of Al and Al 3 Yb are close (0.405 nm and 0.420 nm respectively), indicating there is minimal driving force for causing growth of the Al 3 Yb dispersoids. This low interfacial energy makes the Al 3 Yb dispersoids thermally stable and resistant to coarsening up to temperatures as high as about 842° F. (450° C.). In the alloys of this invention, these Al 3 Yb 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, iron or combinations thereof that enter Al 3 Yb in solution. 
     Lutetium forms Al 3 Lu dispersoids in the aluminum matrix that are fine and coherent with the aluminum matrix. The lattice parameters of Al and Al 3 Lu are close (0.405 nm and 0.419 nm respectively), indicating there is minimal driving force for causing growth of the Al 3 Lu dispersoids. This low interfacial energy makes the Al 3 Lu dispersoids thermally stable and resistant to coarsening up to temperatures as high as about 842° F. (450° C.). In the alloys of this invention, these Al 3 Lu 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, iron or mixtures thereof that enter Al 3 Lu in solution. 
     Gadolinium forms metastable Al 3 Gd dispersoids in the aluminum matrix that are stable up to temperatures as high as about 842° F. (450° C.) due to their low diffusivity in aluminum. The Al 3 Gd dispersoids have an L1 2  structure in the metastable condition and a D0 19  structure in the equilibrium condition. Despite its large atomic size, gadolinium has fairly high solubility in the Al 3 X intermetallic dispersoids (where X is scandium, erbium, thulium, ytterbium or lutetium). Gadolinium can substitute for the X atoms in Al 3 X intermetallic, thereby forming an ordered L1 2  phase which results in improved thermal and structural stability. 
     Yttrium forms metastable Al 3 Y 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 3 Y dispersoids have a low diffusion coefficient which makes them thermally stable and highly resistant to coarsening. Yttrium has a high solubility in the Al 3 X intermetallic dispersoids allowing large amounts of yttrium to substitute for X in the Al 3 X L1 2  dispersoids which results in improved thermal and structural stability. 
     Zirconium forms Al 3 Zr dispersoids in the aluminum matrix that have an L1 2  structure in the metastable condition and D0 23  structure in the equilibrium condition. The metastable Al 3 Zr dispersoids have a low diffusion coefficient which makes them thermally stable and highly resistant to coarsening. Zirconium has a high solubility in the Al 3 X dispersoids allowing large amounts of zirconium to substitute for X in the Al 3 X dispersoids, which results in improved thermal and structural stability. 
     Titanium forms Al 3 Ti 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 3 Ti despersoids have a low diffusion coefficient which makes them thermally stable and highly resistant to coarsening. Titanium has a high solubility in the Al 3 X dispersoids allowing large amounts of titanium to substitute for X in the Al 3 X dispersoids, which result in improved thermal and structural stability. 
     Hafnium forms metastable Al 3 Hf 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 3 Hf dispersoids have a low diffusion coefficient, which makes them thermally stable and highly resistant to coarsening. Hafnium has a high solubility in the Al 3 X dispersoids allowing large amounts of hafnium to substitute for scandium, erbium, thulium, ytterbium, and lutetium in the above mentioned Al 3 X dispersoides, which results in stronger and more thermally stable dispersoids. 
     Niobium forms metastable Al 3 Nb 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 3 X dispersoids than hafnium or yttrium, allowing relatively lower amounts of niobium than hafnium or yttrium to substitute for X in the Al 3 X dispersoids. Nonetheless, niobium can be very effective in slowing down the coarsening kinetics of the Al 3 X dispersoids because the Al 3 Nb dispersoids are thermally stable. The substitution of niobium for X in the above mentioned Al 3 X dispersoids results in stronger and more thermally stable dispersoids. 
     Iron forms Al 6 Fe dispersoids in the aluminum matrix in the metastable condition, and forms Al 3 Fe dispersoids in the equilibrium condition. Iron has a little solubility in aluminum matrix in the equilibrium condition which can be extended significantly by a rapid solidification process. Iron can be very effective in slowing down the coarsening kinetics because the Al 6 Fe dispersoids are thermally stable due to its very low diffusion coefficient in aluminum. Iron provides solid solution and dispersion strengthening in aluminum. 
     The amount of nickel present in the matrix of this invention may vary from about 4 to about 25 weight percent, more preferably from about 6 to about 20 weight percent, and even more preferably from about 8 to about 15 weight percent. 
     The amount of cerium present in the matrix of this invention may vary from about 2 to about 25 weight percent, more preferably from about 4 to about 20 weight percent, and even more preferably from about 6 to about 15 weight percent. 
     The amount of scandium present in the alloys of this invention, if any, may vary from about 0.1 to about 4 weight percent, more preferably from about 0.1 to about 3 weight percent, and even more preferably from about 0.2 to about 2.5 weight percent. The Al—Sc phase diagram shown in  FIG. 3  indicates a eutectic reaction at about 0.5 weight percent scandium at about 1219° F. (659° C.) resulting in a solid solution of scandium and aluminum and Al 3 Sc 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 2  intermetallic Al 3 Sc 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 3 ° C./second. Alloys with scandium in excess of the eutectic composition cooled normally will have a microstructure consisting of relatively large Al 3 Sc dispersoids in a finally divided aluminum-Al 3 Sc eutectic phase matrix. 
     The amount of erbium present in the alloys of this invention, if any, may vary from about 0.1 to about 20 weight percent, more preferably from about 0.3 to about 15 weight percent, and even more preferably from about 0.5 to about 10 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 3 Er 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 cooled normally will have a microstructure consisting of relatively large Al 3 Er dispersoids in a finely divided aluminum-Al 3 Er eutectic phase matrix. 
     The amount of thulium 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 10 weight percent, and even more preferably from about 0.4 to about 6 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 3 Tm dispersoids in the aluminum matrix that have an L1 2  structure in the equilibrium condition. The Al 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 2  intermetallic Al 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 3 ° C./second. 
     The amount of ytterbium present in the alloys of this invention, if any, may vary from about 0.1 to about 25 weight percent, more preferably from about 0.3 to about 20 weight percent, and even more preferably from about 0.4 to about 10 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 3 Yb 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. 
     The amount of lutetium present in the alloys of this invention, if any, may vary from about 0.1 to about 25 weight percent, more preferably from about 0.3 to about 20 weight percent, and even more preferably from about 0.4 to about 10 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 3 Lu 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. 
     The amount of gadolinium present in the alloys of this invention, if any, may vary from about 2 to about 30 weight percent, more preferably from about 4 to about 25 weight percent, and even more preferably from about 6 to about 20 weight percent. 
     The amount of yttrium present in the alloys of this invention, if any, may vary from about 2 to about 30 weight percent, more preferably from about 4 to about 25 weight percent, and even more preferably from about 6 to about 20 weight percent. 
     The amount of zirconium present in the alloys of this invention, if any, may vary from about 0.5 to about 5 weight percent, more preferably from about 1 to about 4 weight percent, and even more preferably from about 1 to about 3 weight percent. 
     The amount of titanium present in the alloys of this invention, if any, may vary from about 0.5 to about 10 weight percent, more preferably from about 1 to about 8 weight percent, and even more preferably from about 1 to about 4 weight percent. 
     The amount of hafnium present in the alloys of this invention, if any, may vary from about 0.5 to about 10 weight percent, more preferably from about 1 to about 8 weight percent, and even more preferably from about 1 to about 4 weight percent. 
     The amount of niobium present in the alloys of this invention, if any, may vary from about 0.5 to about 5 weight percent, more preferably from about 1 to about 4 weight percent, and even more preferably from about 1 to about 3 weight percent. 
     The amount of iron present in the matrix of this invention may vary from about 0.5 to about 15 weight percent, more preferably from about 1 to about 10 weight percent, and even more preferably from about 2 to about 8 weight percent. 
     Forming the amorphous structure of this invention enhances the strength of the alloys, whereas ductility, fracture toughness and thermal stability are increased by the dispersed, fine, coherent L1 2  particles in the microstructure. 
     Exemplary aluminum alloys of this invention include, but are not limited to (in weight percent): 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-4)Sc-(2-30)Gd; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-20)Er-(2-30)Gd; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-15)Tm)-(2-30)Gd; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Lu)-(2-30)Gd; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Yb-(2-30)Gd; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-4)Sc-(2-30)Y; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-20)Er-(2-30)Y; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-15)Tm)-(2-30)Y; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Lu)-(2-30)Y; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Yb-(2-30)Y; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-4)Sc-(0.5-5)Zr; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-20)Er-(0.5-5)Zr; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-15)Tm)-(0.5-5)Zr; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Lu)-(0.5-5)Zr; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Yb-(0.5-5)Zr; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-4)Sc-(0.5-10)Ti; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-20)Er-(0.5-10)Ti; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-15)Tm-(0.5-10)Ti; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Lu-(0.5-10)Ti; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Yb-(0.5-10)Ti; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-4)Sc-(0.5-10)Hf; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-20)Er-(0.5-10)Hf; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-15)Tm-(0.5-10)Hf; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Lu)-(0.5-10)Hf; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Yb-(0.5-10)Hf, 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-4)Sc-(0.5-5)Nb; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-20)Er)-(0.5-5)Nb; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-15)Tm-(0.5-5)Nb; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Lu)-(0.5-5)Nb; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Yb-(0.5-5)Nb; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-4)Sc-(0.5-15)Fe; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-20)Er)-(0.5-15)Fe; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-15)Tm-(0.5-15)Fe; 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Lu)-(0.5-15)Fe; and 
     about Al-(4-25)Ni-(2-25)Ce-(0.1-25)Yb-(0.5-15)Fe. 
     In the inventive aluminum based alloys disclosed herein, scandium forms an equilibrium Al 3 Sc intermetallic dispersoid that has an L1 2  structure that is an ordered face centered cubic structure with the Sc atoms located at the corners and aluminum atoms located on the cube faces of the unit cell. 
     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 that about 0.1 weight percent chromium, 0.1 weight percent manganese, 0.1 weight percent vanadium and 0.1 weight percent cobalt. The total quantity of additional elements should not exceed about 1% by weight, including the above listed impurities and other elements. 
     These aluminum alloys may be made by rapid solidification processing. The rapid solidification process should have a cooling rate greater that 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. 
     More exemplary aluminum alloys of this invention include, but are not limited to (in weight percent): 
     about Al-(6-20)Ni-(4-20)Ce-(0.1-3)Sc-(4-25)Gd; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-15)Er-(4-25)Gd; 
     about Al-(6-20)Ni-(4-20)Ce-(0.2-10)Tm)-(4-25)Gd; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Lu)-(4-25)Gd; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Yb-(4-25)Gd; 
     about Al-(6-20)Ni-(4-20)Ce-(0.1-3)Sc-(4-25)Y; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-15)Er-(4-25)Y; 
     about Al-(6-20)Ni-(4-20)Ce-(0.2-10)Tm)-(4-25)Y; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Lu)-(4-25)Y; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Yb-(4-25)Y; 
     about Al-(6-20)Ni-(4-20)Ce-(0.1-3)Sc-(1-4)Zr; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-15)Er-(1-4)Zr; 
     about Al-(6-20)Ni-(4-20)Ce-(0.2-10)Tm)-(1-4)Zr; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Lu)-(1-4)Zr; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Yb-(1-4)Zr; 
     about Al-(6-20)Ni-(4-20)Ce-(0.1-3)Sc-(1-8)Ti; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-15)Er-(1-8)Ti; 
     about Al-(6-20)Ni-(4-20)Ce-(0.2-10)Tm-(1-8)Ti; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Lu-(1-8)Ti; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Yb-(1-8)Ti; 
     about Al-(6-20)Ni-(4-20)Ce-(0.1-3)Sc-(1-8)Hf; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-15)Er-(1-8)Hf; 
     about Al-(6-20)Ni-(4-20)Ce-(0.2-10)Tm-(1-8)Hf; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Lu-(1-8)Hf; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Yb-(1-8)Hf; 
     about Al-(6-20)Ni-(4-20)Ce-(0.1-3)Sc-(1-3)Nb; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-15)Er-(1-3)Nb; 
     about Al-(6-20)Ni-(4-20)Ce-(0.2-10)Tm-(1-3)Nb; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Lu-(1-3)Nb; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Yb-(1-3)Nb; 
     about Al-(6-20)Ni-(4-20)Ce-(0.1-3)Sc-(1-10)Fe; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-15)Er)-(1-10)Fe; 
     about Al-(6-20)Ni-(4-20)Ce-(0.2-10)Tm-(1-10)Fe; 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Lu)-(1-10)Fe; and 
     about Al-(6-20)Ni-(4-20)Ce-(0.3-20)Yb-(1-10)Fe. 
     More preferred examples of similar alloys to these are alloys with about 8 to about 15 weight percent nickel and about 6 to about 15 weight percent cerium, and include, but are not limited to (in weight percent): 
     about Al-(8-15)Ni-(6-15)Ce-(0.2-2.5)Sc-(6-20)Gd; 
     about Al-(8-15)Ni-(6-15)Ce-(0.5-10)Er-(6-20)Gd; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-6)Tm-(6-20)Gd; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Lu-(6-20)Gd; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Yb-(6-20)Gd; 
     about Al-(8-15)Ni-(6-15)Ce-(0.2-2.5)Sc-(6-20)Y; 
     about Al-(8-15)Ni-(6-15)Ce-(0.5-10)Er-(6-20)Y; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-6)Tm-(6-20)Y; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Lu-(6-20)Y; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Yb-(6-20)Y; 
     about Al-(8-15)Ni-(6-15)Ce-(0.2-2.5)Sc-(1-3)Zr; 
     about Al-(8-15)Ni-(6-15)Ce-(0.5-10)Er-(1-3)Zr; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-6)Tm-(1-3)Zr; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Lu-(1-3)Zr; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Yb-(1-3)Zr; 
     about Al-(8-15)Ni-(6-15)Ce-(0.2-2.5)Sc-(1-4)Ti; 
     about Al-(8-15)Ni-(6-15)Ce-(0.5-10)Er-(1-4)Ti; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-6)Tm-(1-4)Ti; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Lu-(1-4)Ti; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Yb-(1-4)Ti; 
     about Al-(8-15)Ni-(6-15)Ce-(0.2-2.5)Sc-(1-4)Hf; 
     about Al-(8-15)Ni-(6-15)Ce-(0.5-10)Er-(1-4)Hf; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-6)Tm-(1-4)Hf; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Lu-(1-4)Hf; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Yb-(1-4)Hf; 
     about Al-(8-15)Ni-(6-15)Ce-(0.2-2.5)Sc-(1-3)Nb; 
     about Al-(8-15)Ni-(6-15)Ce-(0.5-10)Er)-(1-3)Nb; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-6)Tm-(1-3)Nb; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Lu)-(1-3)Nb; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Yb-(1-3)Nb; 
     about Al-(8-15)Ni-(6-15)Ce-(0.2-2.5)Sc-(2-8)Fe; 
     about Al-(8-15)Ni-(6-15)Ce-(0.5-10)Er)-(2-8)Fe; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-6)Tm-(2-8)Fe; 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Lu)-(2-8)Fe; and 
     about Al-(8-15)Ni-(6-15)Ce-(0.4-10)Yb-(2-8)Fe. 
     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.