ALUMINUM-CHROMIUM ALLOY AND PRODUCTION THEREOF

Abstract: An aluminum-chromium alloy having a high strength and excellent resistances to heat, corrosion, etc., which comprises 10 to 25 at. % of chromium, 0.1 to 5.0 at. % of iron and/or nickel, and the balance of substantially aluminum, wherein the total content of chromium and iron and/or nickel is 30 at. % or less. This alloy has a partially or wholly amorphous structure according to X-ray diffractometry. The production process comprises pulverizing the raw material by quench solidification, mechanically grinding the pulverized material, and hot solidifying the amorphous powder thus formed.

Description: SPECIFICATION Title of the Invention Aluminum-Chromium Based Alloy and Method of Preparing the Same Field of the Invention The present invention relates to an aluminum-chromium based alloy and a method of preparing the same, and more particularly, it relates to an aluminum-chromium based alloy which has high strength and is excellent in heat resistance, corrosion resistance and the like, and a method of preparing the same. Background of the Invention Amorphous aluminum alloys are disclosed in Japanese Patent Laying-Open Gazette No. 1-275732, Japanese Patent Publication Gazette No. 64-47831 and Japanese Patent Publication Gazette No. 1-127641, for example. The amorphous aluminum alloys disclosed in these gazettes contain La, or Nb, Ta, Hf, Y and the like as essential alloy contents. An Aℓ-Si-X alloy and an Aℓ-Ce-X alloy are described in Transactions of the Japan Institute of Metals, Vol. 28, No. 12, p. 968. The amorphous alloys disclosed in the aforementioned prior art examples are prepared by a super-rapid solidification method in most cases. As to another method, it is said that an amorphous alloy can be prepared also by a mechanical alloying method. In addition to the aforementioned two methods, a vapor phase deposition method, an electrolytic deposition method, an electron beam irradiation method, an extra-high pressure method and the like are known as methods for obtaining amorphous alloys. However, these methods have not yet been industrialized due to considerable restriction in practice. An amorphous alloy prepared by the super-rapid solidification method or the mechanical alloying method has not satisfied both mechanical and economical properties. In other words, an amorphous alloy having excellent mechanical properties contains high-priced elements. An amorphous alloy containing only low-priced elements has inferior mechanical properties. An amorphous alloy is crystallized by heating. If the crystallization temperature of the amorphous alloy is too low, it is impossible to perform sufficient warm solidification of alloy powder. Also in view of actual employment, it is difficult to use such an amorphous alloy having a low crystallization temperature since the upper limit of available temperatures is lowered. JP-A-63-153 237 discloses an Al-based alloy partly having an amorphous structure, said alloy comprising as additional elements at least one out of Cr, Mn, Fe, Co and Ni in an amount of 4 to 23 atomic percent as well as Si or Ge in an amount of 8 to 54 atomic percent, the additional elements not exceding 67 atomic percent. An object of the present invention is to provide an aluminum-chromium based alloy which can satisfied both mechanical and economical properties. Another object of the present invention is to provide an aluminum-chromium based alloy which has a high crystallization temperature. Still another object of the present invention is to provide a method of preparing an aluminum-chromium based alloy which can satisfy both mechanical and economical properties. A further object of the present invention is to provide a method of preparing an aluminum-chromium based alloy which has a high crystallization temperature. The inventors have found that an aluminum-chromium based alloy containing an amorphous phase can be obtained by preparing an Aℓ-Cr-X based alloy by a novel method. They have further found that the above described aluminum-chromium based alloy containing an amorphous phase has a high crystallization temperature, and is excellent in material characteristics. Such an Aℓ-Cr-X based alloy is also excellent in economical property since low-priced Cr is employed as a raw material. An attempt for obtaining an Aℓ-Cr amorphous alloy is disclosed in Transactions of the Japan Institute of Metals, Vol. 28, No. 8 (1987), p. 679, for example. While a vapor-phase method, i.e., an RF sputtering method, is employed in this prior art, only a quasi-crystalline structure, which is thermodynamically more stable than an amorphous phase, is obtained by this method. In general, it has been recognized that absolutely no amorphous phase is obtained in an Aℓ-Cr based alloy even if a super-rapid solidification method or a mechanical alloying method is employed. As described above, it has been difficult to convert an Aℓ-Cr based alloy to an amorphous state. In order to implement such amorphous conversion of an Aℓ-Cr based alloy, the inventors have attached importance to the following two points: (1) Additional element groups for facilitating amorphous conversion and a novel alloy composition. (2) A novel preparation method including a novel thermomechanical working treatment method implementing conversion to an amorphous state. In order to obtain an Aℓ-Cr based amorphous alloy, combination of such novel alloy composition and novel preparation method is indispensable. An aluminum-chromium based alloy according to the present invention contains 10 to 25 atomic percent of Cr, and 0.1 to 5.0 atomic percent of at least one element selected from a group of Fe and Ni and optionally not more than 30 atomic percent of at least one element selected from Ti, Zr, Si, V, Nb, Mo, W, Mn, Co and Hf. The total content of Cr, and Fe and/or Ni is not more than 30 atomic percent. The rest, apart from impurities, consists of aluminum. This aluminum-chromium based alloy partially or entirely exhibits an amorphous structure by X-ray diffraction or electron beam diffraction. It contains second phase reinforcing materials such as particles, whiskers and short fibers in dispersed states. The aforementioned aluminum-chromium based alloy is prepared by the following method: In one aspect, the method of preparing an aluminum-chromium based alloy comprises a step of obtaining a foil or powder raw material from a melt by a rapid solidification method, a step of obtaining powder, which is converted to an amorphous state, by performing a mechanical grinding treatment or a mechanical working treatment equivalent thereto on the raw material, and a step of performing warm solidification of the amorphous powder. In another aspect, the method of preparing an aluminum-chromium based alloy comprises a step of obtaining aluminum-chromium binary system alloy powder from a melt of an aluminum-chromium binary system alloy by a rapid solidification method, and a step of alloying remaining elements other than aluminum and chromium in the aluminum-chromium binary system alloy powder by a mechanical alloying method. In still another aspect, the method of preparing an aluminum-chromium based alloy comprises a step of obtaining crystalline powder by alloying industrial pure aluminum powder, pure chromium or an aluminum mother alloy containing chromium, and remaining elements other than aluminum and chromium or mother alloys of the elements by a mechanical alloying method, a step of partially or entirely converting the crystalline powder to an amorphous state by a thermal activation annealing treatment, and a step of performing warm solidification of the amorphous powder. Preferred manufacturing methods are disclosed in the dependent claims 3 and 4, 6 and 8 to 10. The additional element groups described in the item (1) are adapted to facilitate formation of an amorphous phase when an aluminum-chromium based alloy is prepared by the method described in the item (2). In particular, it is conceivable that Fe and Ni of the first group are essential elements for converting the aluminum-chromium based alloy to an amorphous state. Ti, Zr, Si, V, Nb, Mo, W, Mn, Co and Hf of the second group are elements for improving various characteristics of the alloy without much inhibiting amorphous conversion of the aluminum-chromium based alloy. While no clarification has been made as to what metallurgical action the elements of the first group have on the aluminum-chromium based alloy, it is conceivable that presence of Fe and Ni hinders immediate transition from a simply mixed state, which is thermodynamically most instable, or a supercooled liquid, which is in a next instable state, to a crystalline phase, which is an equilibrium stable phase, and provides an opportunity for remaining in a metastable amorphous phase. The upper limit of the content of the first group elements is 5 atomic percent, since amorphous conversion may be hindered if the content exceeds this limit. The lower limit of the content of the first group elements is 0.1 atomic percent, since no effect of amorphous conversion is attained if the content is less than this limit. In consideration of relation between the first group element(s) of Fe and/or Ni and Aℓ-Cr, which are basic alloys, a preferable content of Cr is 10 to 25 atomic percent. If the content of Cr is not more than 10 atomic percent, mechanical properties of the aluminum-chromium based alloy are deteriorated and amorphous conversion is hard to occur. If the Cr content exceeds 25 atomic percent, lightweightness is damaged and characteristics for serving as a practical material are also deteriorated in view of toughness and the like. Further, amorphous conversion is hard to occur. In order to facilitate amorphous conversion without damaging lightweightness of the aluminum-chromium based alloy, the total content of Cr, and Fe and/or Ni must be not more than 30 atomic percent. While relation between the function of the second group elements consisting of Ti, Zr, Si, V, Nb, Mo, W, Mn, Co and Hf and the mechanism of amorphous conversion is not clear, an effect of improving physical, chemical or mechanical properties of the aluminum-chromium based alloy without hindering amorphous conversion is attained upon addition of the second group elements. If the content of the second group elements exceeds 30 atomic percent, however, original characteristics of the Aℓ-Cr based alloy are damaged. There is not necessarily a fixed criterion as to verification of an amorphous material. X-ray diffraction is the simplest method for deciding whether or not a material is amorphous. When a prepared alloy is subjected to X-ray diffraction, a sharp diffraction peak appears from a crystal plane if the alloy is crystalline. If no such sharp diffraction peak appears but something like a trace of an extremely spread diffraction peak is recognized, it is possible to decide that the material is macroscopically amorphous. Electron beam diffraction is a method for more macroscopically confirming presence of an amorphous phase. When a structure specified by observation with a transmission electron microscope is diffracted with electron beams, it is possible to decide this structure as being amorphous if the so-called halo pattern, which is not recognized in a crystalline material, vaguely appears with appearance of no regular diffraction line nor diffraction point group. In addition to X-ray diffraction and electron beam diffraction, there is still another method for deciding whether or not a material is amorphous. For example, DSC (differential scanning calorimeter) analysis is adapted to decide whether or not a material has been amorphous with exothermic reaction in crystallization by heating. However, this analysis method is not suitable for state analysis of the inventive alloy since it requires heating. In the DSC analysis, further, it is difficult to make a correct decision when a part of the material is amorphous and the rest is crystalline. On the other hand, an amorphous phase can be identified by electron beam diffraction with extremely good sensitivity since it is possible to specify the structure in nanometer units. Thus, the essential condition of the present invention has been set in that the aluminum-chromium based alloy has an amorphous structure which is identified by X-ray diffraction or electron beam diffraction. A method of preparing an amorphous phase according to the present invention is different from conventional methods, and classified into the following two methods. It is possible to obtain an amorphous phase by either method. The first method is adapted to produce an amorphous phase by performing a mechanical grinding treatment on powder or foil which is obtained by a rapid solidification method. The rapid solidification method has frequently been used as a method of obtaining an amorphous phase. As to an Aℓ-Cr based alloy, however, only a quasi-crystalline phase, which is close to an amorphous phase, has been obtained even if the same was rapidly solidified under the best conditions. The inventors have found that it is possible to thermodynamically convert this quasi-crystalline phase to an amorphous phase by mechanically grinding the same. The material may not necessarily have a quasi-crystalline structure before the same is subjected to a mechanical grinding treatment. However, it is preferable to obtain the material to be subjected to mechanical grinding treatment by the rapid solidification method. According to the rapid solidification method, it is possible to implement such a state that Aℓ atoms and Cr atoms, which are principal elements, are homogeneously mixed as primitively as possible without forming coarse intermetallic compounds or the like. Throughout this specification, rapid solidification means that the solidification rate is at least 10³ K/sec., which is a solidification rate attained by a general atomizing method, a splat cooling method or the like. With increase of the solidification rate, the solidified structure of the Aℓ-Cr based alloy is refined and supersaturated dissolution of elements such as Cr in Aℓ progresses to cause refinement of intermetallic compounds, and finally a quasi-crystalline structure starts to appear, so that the entire alloy enters a quasi-crystalline state in the end. Amorphous conversion by mechanical grinding is facilitated with increase of the solidification rate. This is because the thermodynamic state of an intermediate product gradually approaches the state of an amorphous phase with increase of the solidification rate. The inventors have found that a remarkable effect is attained by performing mechanical grinding in an Aℓ-Cr based alloy. Namely, milling, mixing and adhesion/aggregation of powder are repeated by mechanical working so that the interior of the powder is homogeneously mixed not only in macroscopic units but also in atomic units and thermodynamically activated into an extremely instable state by increase of grain boundary energy caused by refinement and lamination as the result, and phase transition from such an instable state to a metastable amorphous phase is further enabled. In the aforementioned first method, the first group elements and/or the second group elements may be added in rapid solidification or in mechanical grinding. The first group elements are preferably added in mechanical grinding since it is easier to add the same in mechanical grinding than in rapid solidification. It is also preferable to add a high-melting point element or an oxidizable element in mechanical grinding, in order to avoid a problem of dissolution. Difference between mechanical alloying (MA) and mechanical grinding (MG) is now described. Mechanical alloying is a treatment which is adapted to perform complex working processes such as mechanical mixing, pulverization and aggregation on at least one type of raw material powder containing elements for forming the composition of the target alloy so that individual particles have the target alloy composition as well as microscopically homogeneous structures. On the other hand, mechanical grinding is a treatment which is adapted to perform complex working processes such as mechanical working, pulverization and aggregation on alloy powder having the composition of the target alloy, thereby introducing distortion, lattice defects etc. into the alloy powder. While mechanical alloying changes the alloy components of the powder, mechanical grinding is not mainly directed to change the alloy components. Although contamination of unavoidable impurities may be caused also in mechanical grinding, such contamination is not a principal object. Comparing mechanical alloying and mechanical grinding with each other, these treatments have different starting raw materials. As to actual operations, however, these treatments can be performed with absolutely identical apparatuses and conditions. For example, a high-energy ball mill called an attriter, a general ball mill, a planetary ball mill, a vibrating mill, a centrifugal mill (angmill) or the like may be employed for both mechanical alloying and mechanical grinding. In the second method according to the present invention, the final composition alloy is not obtained through a dissolution step. Namely, the second method according to the present invention is a novel method of obtaining an amorphous phase, which cannot be obtained by mechanical alloying alone, by preparing crystalline powder which is microscopically and atomically homogeneously mixed as an intermediate raw material by mechanical alloying and thereafter performing a thermal activation annealing treatment on this powder. Although it is known that an amorphous phase can be produced by mechanical alloying alone depending on alloy components, the composition range thereof is extremely restricted. When an amorphous phase is heated, the same is ready for transition to a crystalline phase, which is an essentially stable system. Therefore, conversion of a material, which is not yet in an amorphous state after mechanical alloying, to an amorphous state by heating is absolutely innovative recognition against common sense. It is already known that forced solid solution and compounding in nanometer units can be implemented by mechanical alloying. After an alloy having the inventive composition is subjected to mechanical alloying, its structure is not an amorphous phase but a crystalline phase. This crystalline phase, which is a mixture of a compound group having compositions displaced from those of stoichiometric compounds, is in a thermodynamically high free energy state as compared with a stable stoichiometric compound having the lowest thermodynamic free energy, and at a level slightly higher than the free energy level of an amorphous phase. Thus, the inventors have found that it is possible to slightly reduce the free energy level of such a crystalline phase to convert the same to a metastable amorphous phase by performing a thermal activation annealing treatment after mechanical alloying. In order to obtain a homogeneous intermediate raw material, it is necessary to use industrial pure aluminum powder, pure chromium or an aluminum mother alloy containing chromium, and other alloying elements or mother alloys of these elements. In mechanical alloying, which indispensably requires appropriate balance between cold welding, i.e., seizability, and crushing/dispersion of hard brittle powder, combination of the aforementioned raw materials is important. The thermal activation annealing treatment may be performed during a warm solidification process, or independently of such a warm solidification process. It is preferable to perform the thermal activation annealing treatment in the powder state in view of a further homogeneous treatment, while the thermal activation annealing treatment is preferably performed during the warm solidification process in view of the economical property. In either case, it is necessary for this thermal activation annealing treatment to set an optimum temperature in a temperature range of 400 to 800 K as well as to select an optimum holding time, in response to the alloy to be treated. According to either one of the aforementioned first and second methods, it is possible to obtain an amorphous phase. Either method may be arbitrarily selected. It is preferable to select either method in response to easiness of preparation of the raw material powder as well as preparation of the intermediate raw material powder. In the case of an alloy which is hard to dissolve, for example, it is preferable to obtain alloy powder having a desired composition by preparing the powder not by a rapid solidification method but by a mechanical alloying method. When an extremely long time is required for homogenization or a composition is oxidized by mechanical alloying, or a quasi-crystalline structure is obtained by rapid solidification, it is preferable to prepare alloy powder by rapid solidification. In either method, 500 to 5000 p.p.m. of oxygen is unavoidably contained. While it has not yet been clarified as to whether or not the contained oxygen contributes to formation of the amorphous phase, there is no evidence which is deniable of such contribution. As to a powder solidification method of the present invention, it is possible to employ warm powder extrusion, powder welding, powder forging or the like, which has been used in general. More preferably, a warm solidification treatment is performed at a temperature which is higher than the glass transition point of the amorphous phase and lower than its crystallization temperature, in view of characteristics of the amorphous phase. When the treatment is performed under this temperature condition, glass fluidity is utilized and it is possible to effectively solidify/form the powder into a precise/complicated configuration. The aluminum-chromium based alloy may be used as a matrix, to contain second phase reinforcing materials such as particles, whiskers and short fibers in dispersed states. An aluminum-chromium based alloy containing a reinforcing dispersed layer will have more excellent composite functions. In this case, it is possible to improve strength of boundary by performing compounding through solidification utilizing glass fluidization, in particular. Brief Description of the Drawings Figs. 1A and 1B are typical diagrams showing free energy levels of binary system based alloys at arbitrary temperatures TK. Fig. 2 shows X-ray photographs showing the crystal structure of Aℓ-15%Cr powder which was annealed at 740 K after the same was subjected to mechanical alloying for 1000 hours. Fig. 3 shows an X-ray diffraction pattern of Aℓ-15%Cr powder which was annealed at 740 K and 920 K after the same was subjected to mechanical alloying for 1000 hours. Fig. 4 is an X-ray diffraction patten of pulverized powder of rapidly solidified Aℓ-20at.%Cr foil, which was subjected to mechanical grinding for 300 hours, around heating. Fig. 5 is a DSC (differential scanning calorimeter) analysis diagram of pulverized powder of rapidly solidified Aℓ-20at.%Cr foil, which was subjected to mechanical grinding, in continuous heating. Examples The following treatments Al to C5 were performed on raw materials having blending/compositions shown in Table 1. Table 2 shows the processes and characteristics of the as-obtained alloys. The contents of the processes described in the columns of steps 1 and 2 in Table 2 are as follows: A1: preparation of powder by atomizing method using inert gas - treatment by ball mill filled with argon gas (100 hours) A2: preparation of powder by atomizing method using inert gas - mechanical alloying (attriter - 50 hours) A3: preparation of foil member by quench single roll method - ball mill pulverization and ball mill mechanical grinding (1000 hours) B1: mechanical alloying (attriter - 50 hours) ... thermal activation annealing (700 K, 10 hours) C1: CIP forming ... degassing ... filling into can ... extrusion (673 K, 1:10 in extrusion ratio, 8 mm in diameter) C2: lubrication of metallic mold ... cold forming (5 ton/cm²) ... heating in inert gas (700 K, 20 minutes) ... warm forging ... re-sintering (700 K, 1 hour) C3: lubrication of metallic mold ... cold forming (5 ton/cm²) ... thermal activation annealing in inert gas (700 K, 5 hours) ... preheating for forging (673 K, 20 minutes) ... warm forging ... re-sintering (700 K, 1 hour) C4: lubrication of metallic mold ... cold forming ... heating in inert gas (800 K, 30 minutes) ... glass fluidization forming/solidification C5: mixing of reinforcing material ... lubrication of metallic mold ... cold forming (5 ton/cm²) ... heating in inert gas (800 K, 30 minutes) ... glass fluidization forming/solidification Composition Cr Ni Fe Other Element 1 Other Element 2 Al X1 5 0.4 3 baℓ X2 10 0.4 3 baℓ X3 15 0.4 3 baℓ X4 20 0.4 3 baℓ X5 25 0.4 3 baℓ X6 30 0.4 3 baℓ Y1 15 0 0 baℓ Y2 15 6 3 baℓ Y3 15 3 6 baℓ Y4 15 0.4 3 baℓ Z1 20 0.4 3 Ti-5 V-0.25 baℓ Z2 20 0.4 3 Zr-1 Mo-2 baℓ Z3 20 0.4 3 Nb-3 Hf-1 baℓ Z4 20 0.4 3 Si-8 W-2 baℓ Z5 20 0.4 3 Mn-3 Co-1 baℓ W1 15 0.4 3 SiC-Whisker-10 baℓ W2 15 0.4 3 SiC-Powder-10 baℓ W3 15 0.4 3 C Short Fiber-10 baℓ No. Composition Step 1 Step 2 Phase Invention Room Temperature Strength (kg/mm²) Anneal Strength (kg/mm²) After Annealing at 450°C for 100h. Corrosion Resistance After Salt Spray Test 1 X1 A3 crystalline NO 2 X2 A3 amorphous YES 3 X3 A3 amorphous YES 4 X4 A3 amorphous YES 5 X5 A3 amorphous YES 6 X6 A3 crystalline NO 7 Y1 A2 crystalline NO 8 Y2 A2 crystalline NO 9 Y3 A2 crystalline NO 10 Y4 A2 amorphous YES 11 X3 A1 amorphous YES 12 Y4 B1 amorphous YES 13 Z1 A2 amorphous YES 14 Z2 A2 amorphous YES 15 Z3 A2 amorphous YES 16 Z4 A2 amorphous YES 17 Z5 A2 amorphous YES 18 X3 A1 C1 amorphous YES 85 84 no rusting 19 X3 A1 C2 amorphous YES 82 82 20 X3 B1 C3 amorphous YES 81 81 21 X3 A1 C4 amorphous YES 87 86 22 W1 A1 C5 amorphous YES 90 90 23 W2 A1 C5 amorphous YES 85 85 24 W3 A1 C5 amorphous YES 86 86 While abrupt deterioration of characteristics has been recognized in a conventional amorphous alloy following local or instantaneous temperature rise, it is possible to prevent such abrupt deterioration of characteristics following temperature rise in the inventive amorphous alloy since the amorphous state can be maintained up to an extremely high temperature, as clearly understood from Fig. 5. Further, the inventive amorphous alloy has characteristics which are further excellent as compared with those of a conventional crystalline type aluminum-transition element dispersion-strengthened heat resisting alloy. Then, refer to Figs. 1A and 1B showing free energy levels of binary system alloys. When the first method of the present invention is employed, quasi-crystals etc. are activated from a level of C₄ to a C₂ level by mechanical grinding, and thereafter converted to a C₃ level. When the second method of the present invention is employed, the same enter the C₁ to C₂ levels in a mechanical alloying state, and converted to the C₃ level by subsequent heating. In practice, the levels of C₁ to C₂ are present as the result of a mixture of non-stoichiometric compounds (A n-x B m+x ) of crystalline materials having displaced compositions of C₆ and C₇, and the composition of A n B m is changed and distributed as A n-x B m+x in a partial view. Referring to Fig. 1B, the peak of the higher temperature side shows transition from the C₃ level to the C₅ level, i.e., energy release following crystallization. X-ray photographs of Fig. 2 show the crystal structure of Aℓ-15%Cr powder, which was subjected to mechanical alloying for 1000 hours and thereafter annealed at 740 K. Fig. 3 shows an X-ray diffraction diagram of Aℓ-15%Cr powder, which was subjected to mechanical alloying for 1000 hours and thereafter annealed at 740 K and 920 K. Fig. 4 shows an X-ray diffraction diagram of pulverized powder of rapidly solidified Aℓ-20at.%Cr foil, which was subjected to mechanical grinding for 30 hours, around heating. Fig. 5 shows a DSC (scanning differential thermal capacity) analysis diagram of pulverized powder of rapidly solidified Aℓ-20at.%Cr foil, which was subjected to mechanical grinding for each time, in continuous heating. Industrial Availability The aluminum-chromium based alloy according to the present invention, which has strength, heat resistance and wear resistance of iron and steel materials and lightweightness of an aluminum alloy as well as corrosion resistance of an amorphous alloy, is applicable to various uses such as an automobile, a domestic electric apparatus, an industrial apparatus, an aircraft, an electronic apparatus, a chemical apparatus, and the like.

Claims: An aluminum-chromium based alloy containing 10 to 25 atomic percent of Cr, optionally not more than 30 atomic percent of at least one element selected from Ti, Zr, Si, V, Nb, Mo, W, Mn, Co and Hf, and 0.1 to 5.0 atomic percent of at least one element selected from a group of Fe and Ni, wherein the total content of said Cr, and said Fe and/or Ni is not more than 30 atomic percent, and the rest, apart from impurities, consists of aluminum, said aluminum-chromium based alloy partially or entirely exhibiting an amorphus structure by X-ray diffraction or electron beam diffraction, characterized in that second phase reinforcing materials such as particles, whiskers and short fibers are contained in dispered states. A method of preparing an aluminum-chromium based alloy according to claim 1 said method comprising: a step of obtaining a foil or powder raw material from a melt by a rapid solidification method, a step of obtaining powder, being converted to an amorphous state, by performing a mechanical grinding treatment or a mechanical working treatment equivalent thereto on said raw material, and a step of performing warm solidification of said amorphous powder. A method of preparing an aluminum-chromium based alloy in accordance with claim 2, wherein said raw material powder obtained by said rapid solidification method partially has a quasi-crystalline structure. A method of preparing an aluminum-chromium based alloy in accordance with claim 2 or 3, wherein said warm solidification treatment is performed at a temperature being higher than the glass transition point of said amorphous phase and lower than its crystallization temperature. A method of preparing an aluminum-chromium based alloy, according to claim 1 said method comprising: a step of obtaining aluminum-chromium binary system alloy powder from a melt of an aluminum-chromium binary system alloy by a rapid solidification method, and a step of alloying remaining elements other than aluminum and chromium in said aluminum-chromium binary system alloy powder by a mechanical alloying method. A method of preparing an aluminum-chromium based alloy in accordance with claim 5, wherein said aluminum-chromium binary system alloy powder obtained by said rapid solidification method partially or entirely has a quasi-crystalline structure. A method of preparing an aluminum-chromium based alloy, according to claim 1 said method comprising: a step of obtaining crystalline powder by alloying industrial pure aluminum powder, pure chromium or an aluminum mother alloy containing chromium, and remaining elements other than aluminum and chromium or mother alloys of said elements by a mechanical alloying method, a step of partially or entirely converting said crystalline powder to an amorphous state by a thermal activation annealing treatment, and a step of performing warm solidification of said amorphous powder. A method of preparing an aluminum-chromium based alloy in accordance with claim 7, wherein said amorphous conversion step and said warm solidification step are simultaneously carried out. A method of preparing an aluminum-chromium based alloy in accordance with claim 7 or 8, wherein said thermal activation annealing treatment is performed in a temperature range of 400 to 800 K. A method of preparing an aluminum-chromium based alloy in accordance with claim 7, 8 or 9, wherein said warm solidification treatment is performed at a temperature being higher than the glass transition point of said amorphous phase and lower than its crystallization temperature.

Inventors: KOBAYASHI KOJIRO, TAKEDA YOSHINOBU ITAMI WORKS, KOBAYASHI, KOJIRO, TAKEDA, YOSHINOBU, ITAMI WORKS
Applicants: SUMITOMO ELECTRIC INDUSTRIES, SUMITOMO ELECTRIC INDUSTRIES, LTD.
Application year: 1991
Main classification: C22C1
IPC codes: C22F1, B22F1, B22F3, B22F9, C22C45, C22C1