High-strength aluminum-based alloy, and compacted and consolidated material thereof

Abstract: An aluminum-based alloy having a high strength, a high heat resistance, an excellent toughness and a high specific strength, which has a composition represented by any one of the following general formulae: Al bal Ni a M 1b , Al bal Ni a M 1b M 2c , Al bal Ni a M 1b Q d , and Al bal Ni a M 1b M 2c Q d , wherein M₁ represents at least one element selected from among V, Cr, Mn, Co and Mo, M₂ represents at least one element selected from among Nb, Ta and Hf, Q represents at least one element selected from among Mg, Cu and Zn and a, b, c and d are, in atomic %, 5 ≦ a ≦ 10, 0.1 ≦ b ≦ 5, 0.1 ≦ c ≦ 5 and 0.01 ≦ d ≦ 4. Compacted and consolidated materials are produced by compacting and consolidating a quench-solidified aluminum-based alloy represented by any one of the above-defined formulae.

Description: BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength aluminum-based alloy having a high strength, a high ductility and a high specific strength and to a compacted and consolidated aluminum-based alloy material produced by compacting and consolidating the alloy. 2. Description of the Prior Art An aluminum-based alloy having a high strength and a high heat resistance has heretofore been produced by the liquid quenching process or other similar rapid solidification processes. In particular, such a rapidly solidified aluminum-based alloy is disclosed in Japanese Patent Laid-Open No. 275732/1989. A rapidly solidified aluminum-based alloy is amorphous or microcrystalline and an excellent alloy having a high strength, a high heat resistance and a high corrosion resistance. Although the aluminum-based alloy disclosed in Japanese Patent Laid-Open No. 275732/1989 is an excellent alloy having a high strength, a high heat resistance and a high corrosion resistance and is excellent also in the workability when it is used as a high-strength material, there is room for improvement when it is used as a material in which a high toughness and a high specific strength are required. The above-described alloy is an alloy having a high strength, a heat resistance and a high corrosion resistance, and has excellent workability when it is prepared in a powdery or flaky form by the liquid quenching process and subjected as a raw material to various working processes to give a final product, that is, when a product is prepared through primary working only. However, when a consolidated material is formed from the powder or flakes as the raw material and further worked, that is, subjected to a secondary working, there is room for improvement in workability and retention of excellent properties of the material after the working. Chemical abstracts, vol. 104, no. 4, January 27, 1986, abstract no. 22818r discloses eutectic (in wt%) Al-6% Ni compositions with ternary elements such as 0.5 % Cu, Fe and Mg, 0.2 % Ti and 1 % Cr and Mn. JP-A-62230943 discloses heat-resistant, rapidly solidified Al-alloys containing (in wt%) 3-12 Ni, 0.03 Mn and at least one of 0.02-1 Cr, 0.02-0.7 Zr, 0.03-0.7 V, 0.03-1 Co, 0.08-1 Fe and 0.02-0.5 Ti. Accordingly, an object of the present invention is to provide an aluminum alloy having a high strength, a high heat resistance, a high specific strength and an excellent toughness while maintaining a strength necessary for a structural member required to have a high reliability, and to provide a compacted and consolidated material of an aluminum-based material which enables secondary working (extrusion, machining, etc.) to be easily conducted and excellent properties inherent in the raw material to be retained, even after the working. SUMMARY OF THE INVENTION In order to solve the above-described problem, the first aspect of the present invention is directed to a high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo and a and b are, in atomic %, 6 ≤ a ≤ 10 and 0.1 ≤ b ≤ 5. The second aspect of the present invention is directed to a high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b M 2c wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, M 2 represents at least one element selected from among Nb, Ta and Hf and a, b and c are, in atomic %, 5 ≤ a ≤ 10, 0.1 ≤ b ≤ 5 and 0.1 ≤ c ≤ 5. The third aspect of the present invention is directed to a high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b Q d wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, Q represents at least one element selected from among Mg, Cu and Zn and a, b and d are, in atomic %, 6 ≤ a ≤ 10, 0.1 ≤ b ≤ 5 and 0.01 ≤ d ≤ 4. The fourth aspect of the present invention is directed to a high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b M 2c Q d wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, M 2 represents at least one element selected from among Nb, Ta and Hf, Q represents at least one element selected from among Mg, Cu and Zn and a, b, c and d are, in atomic %, 5 ≤ a ≤ 10, 0.1 ≤ b ≤ 5, 0.1 ≤ c ≤ 5 and 0.01 ≤ d ≤ 4. The above-described alloys of the first to fourth aspect are preferably composed of a matrix of aluminum or a supersaturated aluminum solid solution and, homogeneously and finely distributed in the matrix, particles made of a stable phase or a metastable phase of various intermetallic compounds formed from the matrix element and other alloying elements and/or various intermetallic compounds formed from other alloying elements themselves. The present invention further provides a compacted and consolidated aluminum-based alloy material having a high strength and obtained by compacting and consolidating a quench-solidified aluminum-based alloy having a composition represented by any one of the above-defined general formulae. The compacted and consolidated aluminum-based alloy is preferably composed of a matrix comprised of aluminum or a supersaturated aluminum solid solution, whose average crystal grain size is 40 to 2000 nm, and, homogeneously distributed in the matrix, particles made of a stable phase or a metastable phase of various intermetallic compounds formed from the matrix element and other alloying elements and/or various intermetallic compounds formed from other alloying elements themselves, the intermetallic compounds having a mean particle size of 10 to 1000 nm. Further, the compacted and consolidated material of the present invention is preferably produced by melting a material having the above-specified composition, quench-solidifying the melt into powder or flakes, compacting the resulting powder or flakes, and press forming and consolidating the compacted powder or flakes into the above-mentioned structure by conventional plastic working. BRIEF DESCRIPTION OF THE DRAWINGS FIGS. 1 to 5 are each a graph showing the relationship between the change in composition in the alloy and its properties. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS The aluminum-based alloy of the present invention can be produced through the rapid solidification of a molten metal of an alloy having the above-described composition by the liquid quench process. The liquid quench process is a process wherein a molten alloy is rapidly cooled and, for example, the single-roller melt-spinning process, twin-roller melt-spinning process, in-rotating-water melt-spinning process, etc., are particularly useful. In these processes, a cooling rate of about 10 2 to 10 8 K/sec can be attained. In producing a thin ribbon material by the single-roller melt-spinning process, twin-roller melt-spinning process or the like, a molten metal is injected through a nozzle into, for example, a copper or steel roll having a diameter of 30 to 300 mm and rotating at a constant speed in the range of from about 300 to 10000 rpm. Thus, various thin ribbon materials having a width of about 1 to 300 mm and a thickness of about 5 to 500 µm can be easily produced. On the other hand, a fine wire material can be easily produced by the in-rotating-water melt-spinning process by injecting a molten metal, by means of a back pressure of an argon gas, through a nozzle into a liquid cooling medium layer having a depth of about 1 to 10 cm and held by means of a centrifugal force within a drum rotating at about 50 to 500 rpm. In this case, the angle of the molten metal ejected through the nozzle to the cooling medium surface is preferably about 60° to 90°, while the relative speed ratio of the ejected molten metal to the liquid cooling medium surface is preferably 0.7 to 0.9. Instead of using the above-described processes, a thin film can be produced by sputtering, and a quenched powder can be produced by various atomization processes, such as a high pressure gas spraying process, or a spray process. The alloy of the present invention can be produced by the above-described single-roller melt-spinning process, twin-roller melt-spinning process, in-rotating-water melt spinning process, sputtering, various atomization processes, spray process, mechanical alloying process, mechanical grinding process, etc. Further, if necessary, the mean crystal grain size and the mean size of the intermetallic compound particles can be controlled by suitably selecting the production conditions. Further, some compositions can provide an unnecessarily fine structure. When the structure is unnecessarily fine, however, it often becomes impossible to attain the ductility necessary for the working. In this case, when the resultant structure is heated, crystals grow above a specified temperature. At that time, various intermetallic compounds precipitate within the crystals. Thus, it is also possible to produce an alloy having a crystal grain size and an intermetallic compound particle size suitable for the present invention also by suitably selecting the heating conditions. In the aluminum-based alloy having a composition represented by the general formula according to the first to fourth aspects, when the values of a, b, c and d are respectively outside the ranges of from 5 to 10%, from 0.1 to 5%, from 0.1 to 5% and from 0.01 to 4%, in terms of atomic %, the alloy becomes so brittle that neither satisfactory toughness nor high strength can be obtained. In other words, no alloy having properties contemplated in the present invention can be produced by quenching means on a commercial scale utilizing the above-described liquid quenching process, etc. More precisely, the Ni element combines with Al to form compounds (for example, Al 3 Ni), which are homogeneously dispersed in the Al matrix to improve the strength, rigidity and heat resistance. In the above-described alloy, when the Ni content is less than 5 atomic %, the matrix cannot be satisfactorily strengthened, while when the Ni content exceeds 10 atomic %, the ductility becomes poor. The M 1 element is at least one element selected from among V, Cr, Mn, Co and Mo and combines with Al to form compounds which are homogeneously and finely dispersed in the Al matrix to increase the strength of the matrix and, at the same time, to improve the heat resistance. In the above-described alloy, when the M 1 element content is less than 0.1 atomic %, the matrix is coarsened to lower the strength. On the other hand, when the M 1 element content exceeds 5 atomic %, the elongation at room temperature lowers to cause a problem in working. The M 2 element is at least one element selected from among Nb, Ta and Hf and, when it is present together with the M 1 element, the strength of the matrix can be further increased, with the heat resistance. In the above-described alloy, when the M 2 element content is less than 0.1 atomic %, the matrix is coarsened to lower the strength. On the other hand, when the M 2 element content exceeds 5 atomic %, the elongation at room temperature lowers, which causes a problem in working. Further, when importance is placed on the elongation of the alloy, both the M 1 element content and the M 2 element content are preferably 5 atomic % or less. Further, in the above-described alloy system, the addition of the M 2 element in a very small amount with respect to the M 1 element is particularly useful from the viewpoint of improving the strength and ductility of the alloy. The Q element is at least one element selected from among Mg, Cu and Zn and combines with Al or between Q elements to form compounds. The addition of the Q element in a very small amount serves to strengthen the matrix to improve the strength and, at the same time, can improve the heat resistance, specific strength and specific elasticity. In the above-described alloy, when the Q element content is less than 0.01 atomic %, the effect of the addition of the Q element cannot be expected. On the other hand, when the content exceeds 4 atomic %, the strength lowers. The compacted and consolidated material of the aluminum-based alloy of the present invention is preferably produced by quench-solidifying a material having the composition represented by any one of the general formulae defined above in the first to fourth aspect, compacting the resultant powder or flakes and subjecting the compacted powder or flakes to press forming and consolidating by conventional plastic working means. In this case, the powder or flake as the raw material should have a mean crystal grain size of 2000 nm or less, and when the intermetallic compounds precipitate, the mean particle size should be 1000 nm or less. The raw material is heated at a temperature of 50 to 600°C in the step of compacting and subjected to forming consolidation to provide the compacted and consolidated material of the present invention. The above-described conventional plastic working means should be interpreted in a broad sense and includes also press forming and powder metallurgy techniques. In the above-described general formulae, when the values of a, b, c and d are respectively limited to 5 to 10%, 0.5 to 5% , 0.5 to 5% and 0.01 to 4% in terms of atomic %, the material has a higher strength at room temperature to high temperatures (particularly 200°C) than that of the conventional (commercially available) high-strength aluminum alloys and a ductility sufficient to withstanding practical working. In the alloy consolidated material of the present invention, Ni element is an element having a relatively small diffusibility in the Al matrix and, when Ni is finely dispersed as an intermetallic compound (for example, Al 3 Ni) in the Al matrix, it has the effect of strengthening the matrix and inhibiting the growth of crystal grains. Thus, it can remarkably improve the hardness and strength of the alloy and stabilize the finely crystalline phase not only at room temperature but also at high temperatures, thus imparting heat resistance. The M 1 element is an element having a small diffusibility in the Al matrix and forms various metastable or stable intermetallic compounds, which contributes to the stabilization of the resultant fine crystalline structure. As with the M 1 element, the M 2 element has a small diffusibility in the Al matrix to form various metastable or stable intermetallic compounds and is present together with the M 1 element to further contribute to the stabilization of the fine crystalline structure. The Q element combines with Al or another Q element to form compounds to strengthen the matrix and, at the same time, to improve the heat resistance. Further, it can improve the specific strength and specific elasticity. In the consolidated material of an aluminum-based alloy according to the present invention, the mean crystal grain size of the matrix is preferably limited to 40 to 2000 nm, because when it is less than 40 nm, the strength is high but the ductility is insufficient and a mean crystal grain size of 40 nm or more is necessary for attaining a ductility sufficient for existing working processes, while when it exceeds 2000 nm, the strength lowers so rapidly that a material having a high strength cannot be produced. In order to produce a material having a high strength, it is preferable that the mean matrix crystal grain size be 2000 nm or less. The mean particle size of the intermetallic compounds is preferably limited to 10 to 1000 nm, because when it is outside the above-described range, the intermetallic compounds do not serve as an element for strengthening the Al matrix. Specifically, when the mean particle size is less than 10 nm, the intermetallic compounds do not contribute to the strengthening of the Al matrix, and when the intermetallic compounds are excessively dissolved in the solid solution form in the matrix, there is a possibility that the material becomes brittle. On the other hand, when the mean particle size exceeds 1000 nm, the size of the dispersed particles becomes too large to maintain the strength and the intermetallic compounds cannot serve as a strengthening element. When the mean particle size is in the above-described range, it becomes possible to improve the Young's modulus, high-temperature strength and fatigue strength. In the compacted and consolidated material of an aluminum-based alloy according to the present invention, the mean crystal grain size and the state of dispersion of the intermetallic compounds can be controlled through proper selection of the production conditions. When importance is given to the strength, the mean crystal grain size of the matrix and the mean grain size of the intermetallic compounds are controlled so as to become small. On the other hand, when importance is given to the ductility, the mean crystal grain size of the matrix and the mean particle size of the intermetallic compounds are controlled so as to become large. Thus, compacted and consolidated materials suitable for various purposes can be produced. Further, when the mean crystal grain size of the matrix is controlled so as to fall within the range of from 40 to 2000 nm, it becomes possible to impart excellent properties as a superplastic working material. The present invention will now be described in more detail with reference to the following Examples. Example 1 Each of the master alloys having a composition (atomic percentage) specified in Table 1 was produced by the melt process in an arc melting furnace, and a thin ribbon (thickness: 20 µm, width: 1.5 mm) was produced therefrom by means of a conventional single-roller liquid quenching apparatus (a melt spinning apparatus). In this case, the roll was a copper roll with a diameter of 200 mm, the number of revolutions was 4000 rpm, and the atmosphere was argon having a pressure of 10 -3 Torr. The ribbons of alloys having the respective compositions specified in Table 1 and produced under the above-described production conditions were examined for their hardness (Hv) and ductility. The hardness is the value (DPN) measured with a microVickers hardness tester under a load of 25 g. The ductility is expressed in terms of Duc (ductile) when the material has a ductility such that it is not broken in a 180° adhesion bending test, while it is expressed in terms of Bri (brittle) when the material has a ductility such that it cannot be applied to the 180° adhesion bending test. The results are given in Table 1. Invention sample No. Composition (at.%) Hardness Hv (DPN) Ductillity Al Ni M 1 M 2 Q 1 balance 10 Cr=0.6 290 Bri 2 balance 9 V=1.6 270 Duc 3 balance 9 Mn=0.5 265 Duc 4 balance 8 Co=2.5 257 Duc 5 balance 8 Cr=1.0 Nb=2.0 260 Duc 6 balance 7 Mo=0.5 Hf=1.0 223 Duc 7 balance 6 V=0.7 212 Duc 8 balance 10 V=1.0, Cr=1.5 Mg=0.2 289 Bri 9 balance 9 Mn=2.0 Cu=2.0 301 Bri 10 balance 8 Cr=0.5 Mg=1.0, Zn=2.0 278 Bri 11 balance 8 Cr=3.0 Hf=1.0 Cu=1.0 235 Duc 12 balance 7 Cr=1.3 Ta=1.0 Mg=2.5 222 Duc 13 balance 6 V=2.2 Cu=2.5 212 Duc 14 balance 8 Mn=2.0 Mg=2.6 212 Duc 15 balance 7 V=3.2, Co=1.0 Cu=2.0 232 Duc 16 balance 6 Mn=2.0 232 Duc As is apparent from Table 1, the alloys of the present invention are materials having excellent hardness and ductility. Further, the thin ribbons produced under the above-described production conditions were observed under TEM (transmission electron microscopy). As a result, it was found that all the samples had a fine crystalline structure composed of a matrix of aluminum or a supersaturated solid solution of aluminum and, homogeneously distributed in the matrix, particles made of a stable phase or a metastable phase of various intermetallic compounds formed from the matrix element and other alloying elements and/or various intermetallic compounds formed from alloying elements themselves. Example 2 Aluminum-based alloy powders having respective predetermined compositions (Al 97.5-x Ni x Cr 2.5 and Al 92-x Ni 8 Cr x ) were prepared using a gas atomizing apparatus. The aluminum-based alloy powders thus produced were filled into a metallic capsule and degassed to prepare billets for extrusion. These billets were extruded at a temperature of 200 to 550°C by an extruder. The mechanical properties (tensile strength and elongation) at room temperature of the extruded materials (consolidated materials) produced under the above-described production conditions are shown in FIGS. 1 and 2. As is apparent from FIG. 1, the tensile strength of the consolidated material at room temperature rapidly increases when the Ni content is 5 atomic % or more, and rapidly lowers when the Ni content exceeds 10 atomic %. Further, it is apparent that, when the Ni content exceeds 10 atomic %, the elongation is small and the minimum elongation (2%) necessary for general working is obtained when the Ni content is 10 atomic % or less. Further, as shown in FIG. 2, the strength of the consolidated material at room temperature begins to increase when the Cr content reaches 0.1 atomic %, and rapidly lowers when the Cr content exceeds 5 atomic %. Further, it is apparent that the elongation lowers when the Cr content exceeds 5 atomic % and the minimum elongation (2%) necessary for general working is obtained when the Cr content is 5 atomic % or less. Example 3 The procedure of Example 2 was repeated to prepare extruded materials (consolidated materials) having compositions respectively represented by the formulae Al 98-x Ni x Cr 1 Nb 1 and Al 91.5-x Ni 7.5 Cr 1 Nb X . The materials were examined for their mechanical properties (tensile strength and elongation). The results are shown in FIGS. 3 and 4. As is apparent from FIG. 3, the tensile strength of the consolidated material at room temperature rapidly increases when the Ni content is 5 atomic % or more and rapidly lowers when the Ni content exceeds 10 atomic %. Further, it is apparent that, when the Ni content exceeds 10 atomic %, the elongation is small and the minimum elongation (2%) necessary for general working is obtained when the Ni content is 10 atomic % or less. Further, as shown in FIG. 4, the strength of the consolidated material at room temperature begins to increase when the Nb content reaches 0.1 atomic %, and rapidly lowers when the Nb content exceeds 4.5 atomic %. Further, it is apparent that the minimum elongation (2%) necessary for general working is obtained when the Nb content is 5 atomic % or less. Further, it is apparent that the strength rapidly lowers when the total content of Nb and Cr exceeds about 5 atomic %. Example 4 The procedure of Example 2 was repeated to prepare extruded materials (consolidated materials) having a composition represented by the formula Al 91.5-x Ni 8.5 Co x . The material was examined for its mechanical properties (tensile strength and elongation). The results are shown in FIG. 5. As is apparent from FIG. 5, the tensile strength of the consolidated material at room temperature begins to increase when the Co content reaches 0.1 atomic % and rapidly lowers when the Co content exceeds 5 atomic %. Further, it is apparent that when the Co content exceeds 5 atomic %, the elongation lowers and the minimum elongation (2%) necessary for general working is obtained when the Co content is 5 atomic % or less. Example 5 The procedure of Example 2 was repeated to prepare extruded materials (consolidated materials) having the compositions specified in the left column of Table 2 and these materials were subjected to measurement of tensile strength at room temperature, tensile strength at a high temperature (200°C), Young's modulus (modulus of elasticity) and hardness as shown in the right column of Table 2. From the results given in Table 2, it is apparent that the consolidated materials of the present invention have an excellent tensile strength at room temperature and a high temperature (200°C), Young's modulus and hardness. Further, the tensile strength is large and the specific gravity is small, so that it is apparent that the consolidated materials of the present invention have a high specific strength. The consolidated materials listed in Table 1 were subjected to measurement of elongation at room temperature to reveal that the elongation exceeds the minimum elongation (2%) necessary for general working. Test pieces for observation under TEM were cut out of the consolidated materials (extruded materials), including consolidated materials of Examples 2 to 4, produced under the above-described production conditions and observation was conducted to determine the crystal grain size of their matrix and particle size of the intermetallic compounds. All the samples were composed of a matrix of aluminum or a supersaturated aluminum solid solution having a mean crystal grain size of 40 to 2000 nm and, homogeneously distributed in the matrix, particles made of a stable phase or a metastable phase of various intermetallic compounds formed from the matrix element and other alloying elements and/or various intermetallic compounds formed from other alloying elements themselves, the intermetallic compounds having a mean grain size of 10 to 1000 nm. As described above, the aluminum-based alloy of the present invention has a high strength and a high heat resistance, which renders it useful as a high specific strength material and, at the same time, has an excellent workability by virtue of its high specific elasticity and high toughness. Further, it can be worked while retaining sufficient strength necessary to structural materials of which a high reliability is required. Further, the compacted and consolidated material of an aluminum-based alloy according to the present invention can be easily subjected to secondary working (extrusion, cutting, etc.) and still retain excellent properties inherent in the raw material, even after the working.

Claims: A high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo and a and b are, in atomic %, 6 ≤ a ≤ 10 and 0.1 ≤ b ≤ 5. A high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b M 2c wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, M 2 represents at least one element selected from among Nb, Ta and Hf and a, b and c are, in atomic %, 5 ≤ a ≤ 10, 0.1 ≤ b ≤ 5 and 0.1 ≤ c ≤ 5. A high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b Q d wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, Q represents at least one element selected from among Mg, Cu and Zn and a, b and d are, in atomic %, 6 ≤ a ≤ 10, 0.1 ≤ b ≤ 5 and 0.01 ≤ d ≤ 4. A high-strength aluminum-based alloy having a composition represented by the general formula: Al bal Ni a M 1b M 2c Q d wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, M 2 represents at least one element selected from among Nb, Ta and Hf, Q represents at least one element selected from among Mg, Cu and Zn and a, b, c and d are, in atomic %, 5 ≤ a ≤ 10, 0.1 ≤ b ≤ 5, 0.1 ≤ c ≤ 5 and 0.01 ≤ d ≤ 4. A high-strength aluminum-based alloy according to Claim 2 or 4, wherein b and c in the general formula are, in atomic %, b + c ≤ 5. A high-strength aluminum-based alloy according to any one of Claims 1 to 5, wherein the aluminum-based alloy is composed of a matrix of aluminum or a supersaturated aluminum solid solution and, homogeneously and finely distributed in the matrix, particles made of a stable phase or a metastable phase of various intermetallic compounds formed from the matrix element and other alloying elements and/or various intermetallic compounds formed from other alloying elements themselves. A compacted and consolidated aluminum-based alloy, which has been produced by compacting and consolidating a quench-solidified material having a composition represented by the general formula: Al bal Ni a M 1b wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo and a and b are, in atomic %, 6 ≤ a ≤ 10 and 0.1 ≤ b ≤ 5. A compacted and consolidated aluminum-based alloy material, which has been produced by compacting and consolidating a quench solidified material having a composition represented by the general formula: Al bal Ni a M 1b M 2c wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, M 2 represents at least one element selected from among Nb, Ta and Hf and a, b and c are, in atomic %, 5 ≤ a ≤ 10, 0.1 ≤ b ≤ 5 and 0.1 ≤ c ≤ 5. A compacted and consolidated aluminum-based alloy material, which has been produced by compacting and consolidating a quench-solidified material having a composition represented by the general formula: Al bal Ni a M 1b Q d wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, Q represents at least one element selected from among Mg, Cu and Zn and a, b and d are, in atomic %, 6 ≤ a ≤ 10, 0.1 ≤ b ≤ 5 and 0.01 ≤ d ≤ 4. A compacted and consolidated aluminum-based alloy, which has been produced by compacting and consolidating a quench-solidified material having a composition represented by the general formula: Al bal Ni a M 1b M 2c Q d wherein M 1 represents at least one element selected from among V, Cr, Mn, Co and Mo, M 2 represents at least one element selected from among Nb, Ta and Hf, Q represents at least one element selected from among Mg, Cu and Zn and a, b, c and d are, in atomic %, 5 ≤ a ≤ 10, 0.1 ≤ b ≤ 5, 0.1 ≤ c ≤ 5 and 0.01 ≤ d ≤ 4. A compacted and consolidated aluminum-based alloy material according to any one of Claims 7 to 10, wherein the compacted and consolidated material has been produced by melting a material having a composition represented by the general formula, quench-solidifying the molten material into powder or flakes, compacting the resultant powder or flakes and subjecting the compacted powder or flakes to press forming and consolidating the compacted powder or flakes by conventional plastic working means. A compacted and consolidated aluminum-based alloy material according to any one of Claims 7 to 11, wherein the compacted and consolidated material is composed of a matrix of aluminum or a supersaturated aluminum solid solution, whose average crystal grain size is 40 to 2000 nm, and, homogeneously distributed in the matrix, particles made of a stable phase or a metastable phase of various intermetallic compounds formed from the matrix element and other alloying elements and/or various intermetallic compounds formed from other alloying elements themselves, the intermetallic compounds having a mean particle size of 10 to 1000 nm.

Inventors: KITA KAZUHIKO, KITA, KAZUHIKO
Applicants: INOE AKIHISA, YKK CORP, INOUE, AKIHISA, YKK CORPORATION
Application year: 1993
Main classification: C22C21
IPC codes: C22C1, B22F9, C22C45, C22C21