WO2010016269A1 - Matériau structurel en aluminium pur avec résistance spécifique élevée solidifié et moulé par un procédé de traitement à grande déformation - Google Patents

Matériau structurel en aluminium pur avec résistance spécifique élevée solidifié et moulé par un procédé de traitement à grande déformation Download PDF

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WO2010016269A1
WO2010016269A1 PCT/JP2009/003795 JP2009003795W WO2010016269A1 WO 2010016269 A1 WO2010016269 A1 WO 2010016269A1 JP 2009003795 W JP2009003795 W JP 2009003795W WO 2010016269 A1 WO2010016269 A1 WO 2010016269A1
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mold
aluminum
workpiece
bent
pressure
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PCT/JP2009/003795
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English (en)
Japanese (ja)
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久保田正広
シアケノン
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学校法人日本大学
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Priority to EP09804756.6A priority Critical patent/EP2324943A4/fr
Priority to US13/058,145 priority patent/US20110189497A1/en
Priority to JP2010523770A priority patent/JP5392727B2/ja
Publication of WO2010016269A1 publication Critical patent/WO2010016269A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • B22F3/204—Continuous compaction with axial pressure and without reduction of section
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
    • B22F1/105—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material containing inorganic lubricating or binding agents, e.g. metal salts
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • B22F2003/202—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding with back pressure
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • B22F2003/208—Warm or hot extruding
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12229—Intermediate article [e.g., blank, etc.]

Definitions

  • the present invention relates to a pure aluminum structural material having a high specific strength solidified and formed by a giant strain processing method and a method for producing the same.
  • Patent Document 1 JP 2007-84876 A, Patent Document 2, JP 2007-98243 A, Patent Document 1). 3 Japanese Patent Laid-Open No. 8-81718). This type of method is used exclusively for recycling business. Further, it is also known that an aluminum simple substance or alloy is pressed by a pressure rod without being melted by heating, and is plastically fluidized to form a rod-shaped formed body (Patent Document 4 Japanese Patent Application Laid-Open No. 2003-181431, Patent Document 5 Japanese Patent Laid-Open No. 2003-181431).
  • aluminum is used as a structural material
  • an aluminum alloy is manufactured and used as described later. This is because aluminum is not sufficient in terms of hardness and compression strain, which are material characteristics as a structural material, compared to an aluminum alloy, and when using aluminum as a structural material, the above-mentioned material characteristics may be used. Limited to cases, due to limited use.
  • a technology for recovering aluminum that is not in an alloy state and improving the characteristics as a structural material is a required technology.
  • the inventors consider that a material processing technique for using aluminum as a structural material is a technique that will be required in the future.
  • Patent Document 6 Japanese Patent Laid-Open No. 63-2111507
  • Patent Document 7 JP-A-4-277605 As a high-purity aluminum tape, a superconductor (Patent Document 7 JP-A-4-277605), an aluminum superconducting wire (Patent Document 8 JP-A-5-74235), an aluminum superconducting material having a specific crystal structure (Patent Document 9) JP-A-7-166283). It can be understood that aluminum has been actively developed due to its excellent properties as a material.
  • Alloys containing aluminum are being actively developed.
  • An alloy containing Al 4 C 3 which is a sintered / processed aluminum base alloy when manufacturing an alloy is known (Japanese Patent Application Laid-Open No. 62-238344).
  • a vacuum hot press (VHP) is employed at a temperature of 450 ° C. to 545 ° C. using powder and methanol, stearic acid or graphite as auxiliary agents.
  • VHP vacuum hot press
  • Patent Document 11 Japanese Patent Laid-Open No. 63-241103
  • a processing agent containing aluminum An aluminum alloy is known that has a movable punch for applying a processing pressure and is firmly bonded by repeatedly applying plastic deformation under pressure in a mold that defines a bulk shape
  • Patent Document 12 JP-A-8-41571. No. 3267269, JP-A-6-271955. It is known to produce a compression-twisted processed structure in which both forward and reverse twists are applied (Patent Document 14, Japanese Patent Application Laid-Open No. 2007-84889).
  • Dispersion strengthening type metal matrix composites in which dispersion strengthening materials such as metal, metal compound or ceramic particles or whiskers are evenly dispersed in the metal dispersion medium of the composite materials have been promoted.
  • dispersion strengthening materials such as metal, metal compound or ceramic particles or whiskers are evenly dispersed in the metal dispersion medium of the composite materials.
  • High pressure casting method A preform of dispersion strengthening material is made, and this is pressurized and impregnated with molten alloy as a dispersion medium of the composite material.
  • Powder processing method An alloy used as a dispersion medium of a composite material is pulverized, the alloy powder and a dispersion strengthening material are mixed, and the alloy powders are bonded together by pressing and extrusion.
  • Mechanical alloying method An alloy used as a dispersion medium of a composite material is pulverized, the powder and dispersion reinforcing material are mixed, and these are mechanically kneaded.
  • Molten metal method An alloy used as a dispersion medium of a composite material is put into a liquid phase state, and a dispersion strengthening material is added thereto and mixed by stirring.
  • Semi-solid or semi-melt method (hereinafter simply referred to as semi-solid method): An alloy as a dispersion medium of a composite material is made into a solid-liquid mixed phase, and a dispersion strengthening material is added thereto and mixed by stirring.
  • the high-pressure casting method for forming a dispersion-strengthening preform, the powder processing method using an alloy powder, and the mechanical alloying method are not preferable because the process becomes complicated and long. Further, it has been pointed out that it is difficult to produce a large composite material by these production methods (Japanese Patent Laid-Open No. 6-172891).
  • the mechanical alloying it is known that mechanical alloying is used as a pretreatment instead of mechanically kneading the alloy elements after the treatment by mixing.
  • a mixed powder of aluminum and titanium in which an intermetallic compound is formed by mechanical alloying is added to and mixed with the aluminium powder, and the compact obtained by compacting the mixed powder is sintered in an inert atmosphere.
  • Patent Document 17 JP-A-4-331 A method for producing an aluminum sintered body (Patent Document 17 JP-A-4-331).
  • the method of injection molding in a semi-molten or molten state of a metal piece facilitates a metal-based composite material with excellent dispersibility by using the stirring effect of a screw in addition to the advantage that the metal can be safely net-shaped. It has the advantage that it can be integrally molded.
  • the metal matrix composite material When the metal matrix composite material is injection-molded, it is necessary to supply it to the injection molding machine with the reinforcing material uniformly dispersed in the metal pieces.
  • Various methods can be considered as this supply method. For example, a method in which a metal piece and ceramic particles or whisker and other reinforcing materials are simultaneously fed from a hopper of an injection molding machine, or a metal material and a reinforcing material are mixed and compression-molded, and then extruded and pelletized. Is used (Patent 18 Japanese Patent Laid-Open No. 6-238422). By injection-molding these raw materials in a semi-molten or molten state, a metal matrix composite material in which a reinforcing material is dispersed in a matrix can be obtained.
  • the Al alloy melt is cast, and the precursor is dispersed in the preform by the heat of the melt.
  • the intermetallic compound is finely dispersed in the Al matrix of the reinforced composite part, and the preform base Al and the molten Al are firmly bonded.
  • Patent Document 20 JP-A-8-3660, Japanese Patent No. 3417666.
  • the carbon nanomaterial 11 and the metal powder 12 are premixed, the carbon nanomaterial 11 and the metal powder 12 are kneaded in earnest by a mechanical alloy method, and the countless carbon nanomaterial 11 is coated on the metal powder 12.
  • the carbon nanocomposite metal powder 13 is filled in the die 15, and the carbon nanocomposite metal powder 13 is pressed and hardened while maintaining a temperature of about 150 ° C. to obtain a preform 17.
  • Patent Document 21 Japanese Patent Application Laid-Open No. 2007-154246.
  • an intermetallic compound powder is produced in advance by mechanical alloying (MA) or the like, and hot pressed under high-temperature and high-pressure conditions together with fibers and / or particles as reinforcing materials. (HP) or hot isostatic pressing (HIP).
  • MA mechanical alloying
  • HP hot isostatic pressing
  • high temperature and high pressure are applied mainly by a powder metallurgical HP method, HIP method, etc. It can be mentioned that it is necessary to densify the composite material by sintering.
  • Non-Patent Document 1 Scripta Materia 53 (2005) p. 1225-1229. Unfortunately, however, satisfactory results as a structural material could not be obtained in terms of characteristics such as Vickers hardness. JP 2007-84876 A JP 2007-98243 A Japanese Patent Laid-Open No. 8-81718 JP 2003-181431 A JP 2003-181431 A JP-A-63-215071 JP-A-4-277605 Japanese Patent Laid-Open No. 5-74235 Japanese Patent Laid-Open No. 7-166283 Japanese Patent Laid-Open No.
  • the problem to be solved by the invention is to provide a novel structural material using high-purity aluminum having characteristics as a structural material using finely powdered aluminum as a workpiece, and a method for producing the structural material.
  • the present inventors made efforts to solve the above problems, and found the following to solve the problems.
  • (1) Filling a bent L-shaped mold with a workpiece made of fine powdered aluminum containing aluminum and unavoidable impurities, and applying pressure from one direction and the other direction of the mold without melting By passing the bent die hole over, the workpiece can be obtained in a state where a huge strain is applied. By repeating this operation, the workpiece becomes in a state where a huge strain is applied and accumulated, and a workpiece having the characteristics of a structural material can be obtained.
  • the workpiece made of fine powdered aluminum containing aluminum and inevitable impurities is filled at the solidification molding temperature in the bent L-shaped mold, and the pressure applied to the workpiece from one direction of the mold is By making the pressure greater than the pressure applied to the workpiece from the other direction, applying pressure to the workpiece from one direction of the mold and the other direction of the mold, and passing through the die hole of the bent L-shaped mold, After forming a workpiece with a huge amount of accumulated strain, it is supplied by recirculation in one direction of the mold and filled into a bent L-shaped mold at a solidification molding temperature.
  • the pressure applied to the workpiece from one direction of the mold is greater than the pressure applied to the workpiece from the pressure in the other direction of the mold, and the pressure applied to the workpiece from one direction of the mold and the other direction of the mold. And pass through the die hole of the bent L-shaped mold. It can be obtained as the processed material giant strains are added storage. By repeatedly performing this operation, it is possible to obtain a workpiece in which a huge strain having the characteristics of a structural material is additionally accumulated.
  • the operation (1) may be specifically performed, and the following processing may be performed continuously.
  • a workpiece obtained by uniformly dispersing stearic acid in finely divided aluminum is filled in an L-shaped mold obtained by bending the workpiece at a solidification molding temperature.
  • the pressure applied to the work material from the direction is greater than the pressure applied to the work material from the pressure in the other direction of the mold, and the work material is bent from one direction of the mold and the other direction of the mold.
  • a workpiece with a large amount of strain applied and accumulated is obtained, and then a workpiece with a large amount of strain applied and accumulated from the other direction of the mold.
  • the workpiece is bent into an L-shaped mold that is bent toward one direction of the mold, and is filled at the solidification temperature.
  • the pressure applied to the workpiece from one direction of the mold is the other direction of the mold.
  • the pressure is lower than the pressure applied to the workpiece from one side of the mold and the other direction of the mold.
  • Luo pressured workpiece the workpiece that giant strain by passing the die hole of the bent L-shaped die is granted accumulation is obtained. By repeatedly performing this operation, it is possible to obtain a workpiece in which a huge strain having the characteristics of a structural material is additionally accumulated.
  • (7) In the operation of (5) or (6), it is necessary to fill an L-shaped mold obtained by bending a workpiece under a solidification molding temperature condition. For this purpose, heating is performed from the outside of the bent L-shaped mold at a temperature equal to or higher than the solidification molding temperature of the workpiece.
  • the solidification molding temperature is 60 ° C. to 350 ° C., and the temperature higher than the solidification molding temperature is achieved by heating from 400 ° C. to 500 ° C. from the outside of the bent L-shaped mold.
  • the aluminum structural material of the present invention composed of aluminum, aluminum carbide and unavoidable impurities obtained from a workpiece obtained by mechanically and uniformly dispersing stearic acid in finely divided aluminum is contained in finely divided aluminum.
  • the material obtained by uniformly dispersing stearic acid in the L-shaped mold is filled into the L-shaped mold, and solidified molding and powerful strain are simultaneously introduced by applying a pressure to the L-shaped mold multiple times.
  • the molding and solidification temperature is possible at a low temperature, it is possible to manufacture the structural material while maintaining the excellent characteristics of the workpiece.
  • a solid phase reaction is induced by the workpiece, and ceramic particles made of aluminum carbide (Al 4 C 3 ) are generated.
  • the material to be processed of the ceramic particles can be obtained as a structural material that maintains high hardness at high temperatures. Further, it is possible to obtain a structural material that can maintain a high compressive stress in a state where the compressive strain is increased. A structural material made of novel aluminum can be obtained.
  • the figure which shows the particle size distribution of aluminum fine powder The figure which shows the apparatus of this invention.
  • An X-ray diffraction diagram showing that a solid phase reaction has not occurred in the workpiece (no solid phase reaction has occurred in the workpiece).
  • a solidified product made of a workpiece heated to a solidification molding temperature of 100 ° C. under a pressure applied to the workpiece to be stirred and mixed in a ball mill for 4 hours is heated at 400 ° C. higher than the solidification molding temperature. Then, the X-ray diffraction diagram showing that the workpiece has undergone a solid-phase reaction.
  • the workpiece obtained by heating the L-shaped mold to a temperature at which the workpiece to be stirred and mixed for 8 PASS can be solidified and molded into a finely powdered aluminum without being previously stirred and mixed in a ball mill.
  • die to the temperature which can be solidified and molded on the conditions where the said pressure was applied is shown.
  • the aluminum structural material composed of aluminum, aluminum carbide and inevitable impurities according to the present invention is a work material obtained by uniformly mixing and dispersing stearic acid in finely divided aluminum, and is bent L-shaped gold
  • the mold is filled at the solidification temperature, and the pressure applied to the workpiece from one direction of the mold is greater than the pressure applied to the workpiece from the other direction of the mold.
  • the aluminum fine powder an aluminum fine powder obtained by an ordinary production method is used. For example, it is manufactured by (ECKA Granules) of Australia.
  • the aluminum fine powder can be obtained by re-particulating aluminum fine powder particles produced by a spraying method.
  • the purity is 99.7% by weight or more of aluminum, 0.10% by weight or less of silicon, 0.20% by weight or less of iron, and 0.02% by weight or less of other components.
  • the particle size distribution of the aluminum fine powder was a maximum particle size of 100 ⁇ m, and 90% or more was 60 ⁇ m or less.
  • the diffraction results are shown in FIG.
  • the adjustment of the workpiece to be processed has an important meaning.
  • the workpiece is a workpiece obtained by uniformly dispersing stearic acid in fine powdered aluminum.
  • Stearic acid is known as a higher fatty acid and is solid at room temperature.
  • the proportion of stearic acid and aluminum fine powder is in the range of 2 to 10% by weight of aluminum fine powder. If it is less than 2% by weight, a sufficient effect cannot be expected. When it exceeds 10% by weight, it is possible to increase the mixing amount of stearic acid, but a special effect cannot be expected.
  • Finely powdered aluminum and stearic acid are pulverized by stirring and mixing processing means in the presence of stearic acid to uniformly mix and disperse finely powdered aluminum and stearic acid, and the workpiece is To manufacture.
  • a ball mill can be used as the stirring and mixing treatment means.
  • a rolling mill or a dry attritor which is a stirring and mixing means, can be used in the same manner.
  • the fine powdered aluminum is The material to be processed can be manufactured by pulverizing in the presence of stearic acid to uniformly mix and disperse fine powdered aluminum and stearic acid.
  • the time required for the stirring pulverization and mixing process is 3 to 8 hours.
  • fine powdered aluminum and solid stearic acid are treated while rotating the rolling ball mill and revolving at the same time so that the stearic acid is uniformly dispersed in the fine powdered aluminum.
  • a workpiece in a state of being pulverized and mixed can be obtained.
  • the time required for stirring and mixing is 3 to 8 hours. It is also called a planetary crusher.
  • a dry attritor is a mixture of finely powdered aluminum and solid stearic acid in a cylindrical container and stirred and pulverized and mixed with the stearic acid uniformly dispersed in the finely powdered aluminum in a state where centrifugal force is applied. is there.
  • the time required for stirring and mixing is 3 to 8 hours.
  • the workpiece of the present invention is obtained by the following operation.
  • a workpiece obtained by uniformly mixing and dispersing stearic acid in finely divided aluminum is filled into a bent L-shaped mold at a solidification molding temperature, and the workpiece is processed from one direction of the mold.
  • the pressure to be applied is larger than the pressure applied to the workpiece from the other direction of the mold, and the die hole of the bent L-shaped mold is pressed by applying pressure to the workpiece from one direction of the mold and the other direction of the mold.
  • Said (1) is as follows.
  • the workpiece is filled in a bent L-shaped mold at a solidification molding temperature, and the pressure applied to the workpiece from one direction of the mold is greater than the pressure applied to the workpiece from the other direction of the mold.
  • Work material in which huge strain is added and accumulated by applying pressure to the work material from one direction of the mold and the other direction of the mold and passing through the die hole of the bent L-shaped mold Is made by passing through a die hole of a bent L-shaped mold to give a work material to which a huge strain is applied and accumulated, and then recirculated and supplied in the one direction of the mold.
  • the pressure is applied to the workpiece from one direction of the mold to a pressure greater than the pressure applied to the workpiece from the other direction of the mold.
  • L-shaped mold bent by applying pressure to the workpiece from one direction of the mold and the other direction of the mold It is repeated to obtain a workpiece of giant strains are added accumulated by passing the die hole.
  • the recirculation in one direction of the mold is taken out as a work material in which a huge strain is additionally accumulated by passing through a die hole of a bent L-shaped mold, and using a connecting means such as a pipe.
  • the mold is supplied in one direction, filled in the initially bent L-shaped mold at the solidification temperature, and the pressure applied to the workpiece from one direction of the mold is the other direction of the mold.
  • the pressure is larger than the pressure applied to the work material from, and the state in which the pressure is applied to the work material from one direction of the mold and the other direction of the mold is repeated. In this case, there is no change in the way of applying pressure.
  • a workpiece obtained by uniformly dispersing stearic acid in finely divided aluminum is filled in an L-shaped mold obtained by bending the workpiece at a solidification molding temperature.
  • the pressure applied to the work material from the direction is greater than the pressure applied to the work material from the pressure in the other direction of the mold, and the work material is bent from one direction of the mold and the other direction of the mold.
  • the pressure applied to the workpiece from one direction of the mold is the other direction of the mold.
  • the pressure is lower than the pressure applied to the workpiece from one side of the mold and the other direction of the mold. Luo pressured workpiece to obtain a workpiece of giant strains are imparted accumulated by passing the die hole of the bent L-shaped mold.
  • the above operation can be repeated. Specifically, it is as follows.
  • the material to which the enormous strain is imparted and accumulated is filled in a bent L-shaped mold at a solidification temperature from the other direction of the mold toward one direction of the mold,
  • the pressure applied to the workpiece from one direction of the mold is lower than the pressure applied to the workpiece from the other direction of the mold, and the pressure is applied to the workpiece from one direction of the mold and the other direction of the mold.
  • the L-shaped mold in which the workpiece is bent toward the other direction of the mold is filled at the solidification molding temperature, and the mold is covered from one direction of the mold.
  • the pressure applied to the workpiece is higher than the pressure applied to the workpiece from the pressure in the other direction of the mold, and the pressure is applied to the workpiece from one direction of the mold and the other direction of the mold, and the direction of the mold From the other direction of the mold, it is made a work material to which a huge strain is imparted and accumulated by passing through a die hole of an L-shaped mold bent toward the other direction of the mold.
  • the work material is filled in the bent L-shaped mold at the solidification molding temperature and applied to the work material from one direction of the mold.
  • the pressure is smaller than the pressure applied to the workpiece from the other direction of the mold, and the L-shape is bent from the other direction of the mold by applying pressure to the workpiece from one direction of the mold and the other direction of the mold.
  • a specific apparatus for performing the above operation can be performed by the apparatus 1 shown in FIG.
  • a workpiece 4 obtained by uniformly dispersing stearic acid in fine powdered aluminum is supplied from one direction 2 of the L-shaped mold and filled into the L-shaped mold.
  • pressures P and PB are applied from one direction 2 and the other direction 3 of the L-shaped mold.
  • the pressure is larger than PB.
  • the workpiece can be brought into a state where pressure is applied in a state of being filled in a bent L-shaped mold.
  • pressure is applied to the workpiece that passes through the bent die hole 5, a huge strain is applied, and the workpiece is changed into a workpiece having high hardness and extruded.
  • a pressure of 100 MPa is applied to PB, and a larger pressure is applied to P.
  • a pressure of 100 MPa is adopted as experience, and sufficient results have been obtained. This pressure does not need to be larger than necessary.
  • the pressure is too small, it is considered that the pressure to push back is not sufficient even if the pressure is applied in the state of filling the L-shaped mold.
  • the pressure depends on the materials used, the number of passes, the lubrication, and the temperature, including the pressures of P and PB, and depends largely on the slip between the powder particles, and varies depending on each condition.
  • the lower limit of PB is 50 MPa, and the upper limit is tried up to about 200 MPa.
  • the upper limit of 200 MPa in this case means a case where a method of applying a certain force is reversed after obtaining a workpiece once.
  • the maximum P was 750 MPa when the PB was 100 MPa.
  • P was 1000 MPa at the maximum.
  • P can employ a pressure of up to 1000 MPa.
  • a workpiece 4 obtained by uniformly dispersing stearic acid in fine powdered aluminum is supplied from the other direction 3 of the L-shaped mold and filled into the L-shaped mold.
  • pressures P and PB are applied from one direction 2 and the other direction 3 of the L-shaped mold.
  • PB is set to a pressure higher than P.
  • a pressure of 100 MPa is applied to P, and a larger pressure is applied to PB.
  • a pressure of 100 MPa is adopted as experience, and sufficient results have been obtained. This pressure does not need to be larger than necessary.
  • the pressure depends on the materials used, the number of passes, the lubrication, and the temperature, including the pressures of P and PB, and depends largely on the slip between the powder particles, and varies depending on each condition. Considering the circumstances, the lower limit for P is 50 MPa, and the upper limit is tried up to about 200 MPa.
  • the upper limit of 200 MPa in this case means a case where the method of applying pressure is reversed after obtaining a workpiece once.
  • the maximum PB was 750 MPa when P was 100 MPa.
  • PB was 1000 MPa at the maximum.
  • PB can employ a pressure of up to 1000 MPa.
  • the L-shaped mold shows a case where the bent state is a right angle.
  • the bending angle can be appropriately selected.
  • the right angle can give the largest distortion.
  • the portion of the L-shaped mold that is bent into the L shape may be curved.
  • the structural material is in the shape of a cylinder, when this operation is repeated, it is effective to shift the angle with respect to the plane on which the workpiece is to be supplied. For example, assuming that the angle to be shifted is 90 degrees, the process is further shifted by 90 degrees. When shifting by 90 degrees, a large strain is averaged over the whole workpiece by performing an integer number of 4 times (referred to as 4PASS), 8 times (referred to as 8PASS), or 12 times (referred to as 12PASS). Can be granted. Also, if the angle to be shifted is 120 degrees, it is performed an integer number of 3. If the structural material is prismatic, the angle to be shifted is changed to 90 degrees or 180 degrees.
  • the shifting angle can be 30 degrees, 60 degrees, 120 degrees, and 180 degrees, and it is effective to perform the operation an integer number of 12, 6, 3, and 2, respectively.
  • L-shaped mold that is bent in a state in which the work material obtained by uniformly dispersing stearic acid in fine powder aluminum is fixed around the structure material that allows the core portion to be taken out By performing the same operation as described above by filling the inside, it can be applied to the entire hollow structural material having a huge strain.
  • a hollow structure such as a hollow columnar shape, a hollow prismatic shape, or a hollow hexagonal columnar shape can be obtained.
  • the operation of changing the workpiece obtained by uniformly dispersing stearic acid in finely divided aluminum into a structural material is not sufficient to simply apply pressure, and a specific material is used to change the workpiece. Requires heating to temperature. If the operation is to obtain a uniform aluminum structural material by melting fine powder aluminum, it is necessary to heat the fine powder aluminum to a temperature higher than the melting temperature of fine powder aluminum. In the operation of the present invention, a melting operation is not used, and the workpiece obtained by uniformly dispersing stearic acid in finely powdered aluminum is L-shaped at a temperature at which it can be solidified and molded under the above-mentioned pressure. It is necessary to heat the mold.
  • heat treatment has been performed so as to be about 400 ° C. for that purpose. It has now been newly found that the operation of the present invention by the present inventors can be achieved by heating to a lower temperature of 60 ° C. to 350 ° C., preferably 100 ° C. to 350 ° C.
  • Heating in the case of recirculating the structural material obtained in (1) is performed as follows.
  • the workpiece is filled in a bent L-shaped mold at a solidification molding temperature, and the pressure applied to the workpiece from one direction of the mold is greater than the pressure applied to the workpiece from the other direction of the mold.
  • a structural material in which huge strain is additionally accumulated by applying pressure to the workpiece from one direction of the mold and the other direction of the mold and passing it through the die hole of the bent L-shaped mold. Then, after passing through the die hole of the bent L-shaped mold, a work material having a huge strain is given and accumulated, and then supplied by recirculation in the one direction of the mold.
  • the bent L-shaped mold is filled at the solidification molding temperature, and the pressure applied to the workpiece from one direction of the mold is set to be greater than the pressure applied to the workpiece from the other direction of the mold. Applying pressure to the workpiece from one direction of the mold and the other direction of the mold, It is repeated to obtain a structural material giant strains are added accumulated by passing the chair holes.
  • the solidification molding temperature is 60 ° C to 350 ° C, preferably 100 ° C to 350 ° C.
  • the temperature is less than 60 ° C., sufficient solidification molding cannot be performed.
  • it exceeds 350 ° C. it is possible to perform solidification molding itself. This means that even if the temperature is higher than necessary, the operation is performed at an unnecessary high temperature.
  • the workpiece in the L-shaped mold obtained by bending the workpiece is maintained at the solidification molding temperature.
  • the bent L-shaped mold is filled with the workpiece under conditions of the solidification molding temperature.
  • the pressure applied to the workpiece from one direction of the mold is greater than the pressure applied to the workpiece from the other direction of the mold, and the pressure is applied to the workpiece from one direction of the mold and the other direction of the mold.
  • the workpiece is passed through a die hole of an L-shaped mold bent from one direction of the mold toward the other direction.
  • the temperature equal to or higher than the solidification molding temperature of the workpiece is 400 ° C to 500 ° C.
  • the temperature is lower than 400 ° C., the solidification molding temperature cannot be sufficiently maintained.
  • the temperature exceeds 500 ° C., it is possible to maintain the solidification molding temperature itself. This means that even if the temperature is higher than necessary, the operation is performed at an unnecessary high temperature.
  • a workpiece By passing the die hole of the bent L-shaped mold of (2) above, a workpiece is provided with a huge strain applied and accumulated, and then from the other direction of the mold toward one direction of the mold. Heating when the operation is reversed is performed as follows.
  • a workpiece obtained by uniformly dispersing stearic acid in the fine powdered aluminum is filled into an L-shaped mold obtained by bending the workpiece under a solidification molding temperature condition.
  • the pressure applied to the workpiece from one direction of the mold is greater than the pressure applied to the workpiece from the other direction of the mold, and the pressure is applied to the workpiece from one direction of the mold and the other direction of the mold. Call.
  • the structural material passes from one direction of the mold through the die hole of the L-shaped mold and proceeds in one direction of the mold, and a huge strain is imparted and accumulated.
  • the work material After being taken out from the other direction of the mold, the work material is filled in a bent L-shaped mold in one direction of the mold at a solidification molding temperature, and the workpiece is taken from one direction of the mold.
  • the pressure applied to the workpiece is set to be smaller than the pressure applied to the workpiece from the pressure in the other direction of the mold, and the pressure is applied to the workpiece from one direction of the mold and the other direction of the mold.
  • the structural material passes through the die hole of the L-shaped mold bent from the other direction of the mold and proceeds toward one direction of the mold, and the structural material is taken out with a large amount of strain applied thereto. This operation is repeated repeatedly.
  • the workpiece is imparted and accumulated with enormous strain by passing through the die hole of the bent L-shaped mold.
  • the solidification molding temperature is 60 ° C to 350 ° C, preferably 100 ° C to 350 ° C.
  • the temperature is less than 60 ° C., sufficient solidification molding cannot be performed.
  • it exceeds 350 ° C. it is possible to perform solidification molding itself. This means that even if the temperature is higher than necessary, the operation is performed at an unnecessary high temperature.
  • An L-shaped mold obtained by bending a workpiece is filled under a solidification molding temperature condition, and the outside of the L-shaped mold is externally heated.
  • the external heating is 400 ° C to 500 ° C. If it is less than 40 ° C., the solidification molding temperature cannot be maintained sufficiently. When the temperature exceeds 350 ° C., it is possible to maintain the solidification molding temperature itself. This means that even if the temperature is higher than necessary, the operation is performed at an unnecessary high temperature.
  • FIG. 5 shows that a workpiece obtained without uniformly dispersing stearic acid in finely powdered aluminum has a solidification molding temperature of 100 ° C. under the above-mentioned pressure, and is 400 ° C. to 500 ° C. higher than the solidification molding temperature.
  • FIG. 6 is an X-ray diffraction diagram showing that no solid phase reaction occurs between aluminum and stearic acid even when heated to ° C.
  • FIG. 6 shows that when a solidified product composed of aluminum and stearic acid heated to a solidification molding temperature of 100 ° C. is heated from 400 ° C. to 500 ° C. higher than the solidification molding temperature, a solid phase reaction occurs between aluminum and stearic acid, aluminum carbide (Al 4 C 3) is an X-ray diffractogram showing that generates. Further, it has been confirmed that a high-hardness structural material having a Vickers hardness exceeding 125 HV can be obtained by continuing heating at 400 ° C.
  • FIG. 3 shows the result of increasing the hardness by heating for 4 hours at 4PASS and 8PASS.
  • 8PASS the result exceeds that of 4PASS.
  • 4PASS material (0hMM) without pulverizing, mixing and stirring in FIG. 3, when the powder and stearic acid are not pulverized and mixed, a solidified molding material is produced through an L-shaped mold, and then 400 ° C. And heating at 500 ° C. does not increase Vickers hardness.
  • FIG. 4 shows a workpiece obtained by heating an L-shaped mold to a temperature at which it can be solidified and molded under the conditions in which the above-mentioned pressure is applied to finely divided aluminum without performing a stirring and mixing process in a ball mill in advance.
  • mold the material which passed 8PASS is shown by the point of hardness.
  • the L-shaped mold is heated to a temperature at which it can be solidified and molded under the conditions in which the pressure is applied to the finely divided aluminum without performing a stirring and mixing process in a ball mill in advance.
  • the work material obtained is the highest, and then the work material obtained in a state where the L-shaped mold is heated to a temperature capable of solidification molding of the work material to be stirred and mixed for 4 hours in a ball mill is 8
  • the workpieces obtained in a state in which the L-shaped mold is heated to a temperature at which the workpieces to be stirred and mixed for 4 hours in a ball mill can be solidified and molded by 4PASS are arranged in this order.
  • the work material to be stirred and mixed for 4 hours in the ball mill and the work material to be stirred and mixed for 4 hours in the ball mill are not subjected to the stirring and mixing process in the ball mill in advance in terms of relative density. It does not exceed the workpiece obtained in a state where the L-shaped mold is heated to a temperature at which it can be solidified and molded under the condition where the pressure is applied to fine powdered aluminum.
  • FIG. 7 shows the relationship between the compressive stress and the compressive strain.
  • a workpiece obtained in a heated state a workpiece obtained by heating the L-shaped mold to a temperature capable of solidifying and molding the workpiece to be stirred and mixed in a ball mill for 4 hours
  • a ball mill 4 shows a comparison of workpieces obtained by heating the L-shaped mold to a temperature at which solidification molding can be performed by 8 PASS for the workpiece to be stirred and mixed for 4 hours.
  • the former is somewhat higher when the L-shaped mold is heated to a temperature at which the workpiece can be solidified with 4 PASS, and both are finely powdered without prior mixing and mixing in a ball mill.
  • the workpiece obtained in a state in which the L-shaped mold is heated to a temperature at which the aluminum can be solidified and molded under the above-described pressure is exhibited a high value of more than two and a half times. It can be understood that the compressive stress increases as the compressive strain increases, and thus increases, and is sufficient as a characteristic of the structural material.
  • the characteristics of the structural material obtained by the present invention are as follows.
  • the aluminum structural material of the present invention composed of aluminum, aluminum carbide and unavoidable impurities obtained from a workpiece obtained by mechanically and uniformly dispersing stearic acid in finely divided aluminum is contained in finely divided aluminum.
  • the material obtained by uniformly dispersing stearic acid in the L-shaped mold is filled into an L-shaped mold, and the compression stress is increased even if the compressive strain increases by the processing operations of the L-shaped mold 4 times and 8 times. As shown in FIG. 7, it can be obtained as having increased characteristics (FIG. 7), and when the heating time is 10 hours to 100 hours, the hardness can be largely maintained (FIG. 3).
  • the measuring method of the Vickers hardness which is an aluminum structure material comprised from the aluminum obtained by this invention, aluminum carbide, and an unavoidable impurity, and a compression test is as follows.
  • the Vickers hardness was measured by polishing the surface of the solidified material, then using a Vickers hardness tester to perform a test load of 1 kg, a holding time of 15 seconds, and measuring 7 times to obtain an average value thereof.
  • the compression test was machined into a cylindrical specimen with a diameter of 3 mm and a height of 3.5 mm for the extruded longitudinal material and at an initial strain rate of 4.76 ⁇ 10 ⁇ 3 s ⁇ 1 at room temperature. Tested.
  • Fig. 5 shows the X-ray diffraction results when the powder that was ball milled for 0 hours was passed in 4 passes and the resulting solidified molding was heated at 400 ° C. This indicates that no solid-phase reaction was observed.
  • FIG. 6 shows the results of X-ray diffraction when the ball milled for 4 hours, the powder is passed through 4 passes, and the solidified material is heated at 400 ° C.
  • a solid phase reaction occurs between aluminum and stearic acid, and aluminum carbide (Al 4 C 3 ) is generated.
  • FIG. 3 shows that when the solidification molding temperature is 100 ° C. and heating is continued at 400 ° C., a high-hardness structural material having a Vickers hardness exceeding 125 HV can be obtained.
  • FIG. 3 shows the results of increasing the hardness by heating at 4 PASS and 8 PASS at a solidification molding temperature of 100 ° C. for 4 hours. In the case of 8PASS, the result exceeds that of 4PASS.
  • the material (0hMM) that was 4PASSed without pulverizing and stirring in the ball mill produced a solidified molding material through an L-shaped mold when the powder and stearic acid were not pulverized and mixed.
  • FIG. 4 is a diagram showing a result of comparing a workpiece obtained without stirring and mixing in a ball mill and a workpiece obtained by stirring and mixing for 4 hours in a ball mill in terms of Vickers hardness. It shows that a workpiece that is stirred and mixed in a ball mill for 4 hours has a higher Vickers hardness than a workpiece that is obtained without stirring and mixing in a ball mill.
  • Comparative Example By filling a bent L-shaped mold with a workpiece made of fine powdered aluminum, which is a conventional method, and passing it through a bent die hole by applying pressure from one direction and the other direction of the mold.
  • the Vickers hardness of the structural material to which the obtained work material is given a large strain is as follows (which treats finely divided aluminum, and stearic acid is uniformly dispersed in finely divided aluminum. (This is not the case for workpieces obtained by processing.) According to the present inventors, Scripta Materialia 53 (2005) p. 125-1229.
  • a structural material obtained by heating an L-shaped mold to a temperature capable of solidifying and molding 4 PASS for a workpiece to be stirred and mixed in a ball mill for 4 hours, and 4 hours in a ball mill The structural material obtained in a state where the L-shaped mold is heated to a temperature capable of solidifying and molding the workpiece to be stirred and mixed with 8 PASS, and the pressure applied to the finely powdered aluminum without previously performing the stirring and mixing in a ball mill.
  • the work material obtained in a state where the L-shaped mold was heated to a temperature at which solidification molding can be performed under the conditions applied was measured, and the result is shown in FIG.
  • the work material obtained in a state in which the L-shaped mold is heated to a temperature at which the material can be solidified with 4 PASS is somewhat higher in the former, and shows a value of about 500 MPa at 4 to 7 ⁇ c /%.
  • the workpiece obtained by heating the L-shaped mold to a temperature at which it can be solidified and molded under the condition in which the pressure is applied to the fine powdered aluminum without previously performing the stirring and mixing treatment in the ball mill is 200 MPa. The degree has changed and is inferior to the former two.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Inorganic Chemistry (AREA)
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  • Powder Metallurgy (AREA)
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Abstract

L'invention porte sur un nouveau matériau structurel produit à partir d'aluminium de haute pureté. Le matériau structurel est obtenu à l'aide d'aluminium en poudre comme matière première. L'invention porte également sur un procédé pour produire le matériau structurel. Le matériau en aluminium structurel est un matériau d'aluminium traité constitué d'aluminium, de carbure d'aluminium et d'impuretés inévitables, et ayant les propriétés d'un matériau d'aluminium structurel, et est obtenu par le fait de conduire de façon successive un procédé comprenant : le compactage d'une matière première obtenue par dispersion uniforme d'acide stéarique dans de l'aluminium en poudre en une matrice de forme L incurvée ; le pressage de la matière première à partir d'une extrémité et de l'autre extrémité de la matrice de telle sorte que la pression appliquée sur la matière première à partir de la première extrémité de la matrice est supérieure à la pression appliquée à la matière première à partir de l'autre extrémité de la matrice ; et le passage de la matière première à travers la cavité de matrice de la matrice en forme de L incurvée pour obtenir ainsi un matériau traité ayant une grande déformation ajoutée et accumulée dans celui-ci.
PCT/JP2009/003795 2008-08-08 2009-08-07 Matériau structurel en aluminium pur avec résistance spécifique élevée solidifié et moulé par un procédé de traitement à grande déformation WO2010016269A1 (fr)

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EP09804756.6A EP2324943A4 (fr) 2008-08-08 2009-08-07 Matériau structurel en aluminium pur avec résistance spécifique élevée solidifié et moulé par un procédé de traitement à grande déformation
US13/058,145 US20110189497A1 (en) 2008-08-08 2009-08-07 Pure-aluminum structural material with high specific strength consolidated by giant-strain processing method
JP2010523770A JP5392727B2 (ja) 2008-08-08 2009-08-07 巨大歪加工法で固化成形した高比強度を有する純アルミニウム構造材料

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Citations (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61143531A (ja) * 1984-10-23 1986-07-01 インコ、アロイス、インタ−ナシヨナル、インコ−ポレ−テツド 分散強化アルミニウム合金の改良された製造法
JPS62238344A (ja) 1986-04-04 1987-10-19 インコ、アロイス、インタ−ナシヨナル　インコ−ポレ−テツド 機械的合金化
JPS63211507A (ja) 1987-02-26 1988-09-02 住友電気工業株式会社 音響・画像機器用導体
JPS63241103A (ja) 1987-03-27 1988-10-06 Idea Res:Kk 金属等の粉体固形化方法
JPH04331A (ja) 1990-04-16 1992-01-06 Fujitsu Ltd アルミニウム複合焼結体の製造方法
JPH04277605A (ja) 1991-03-06 1992-10-02 Toshiba Corp 超電導々体および超電導コイル
JPH0574235A (ja) 1991-02-20 1993-03-26 Furukawa Electric Co Ltd:The アルミニウム安定化超電導線
JPH06172891A (ja) 1992-12-07 1994-06-21 Leotec:Kk 複合材の製造方法
JPH06238422A (ja) 1993-02-19 1994-08-30 Mazda Motor Corp 複合金属部材の製造方法
JPH06271955A (ja) 1993-01-21 1994-09-27 Toyota Central Res & Dev Lab Inc アルミニウム合金の製造方法
JPH07166283A (ja) 1993-07-06 1995-06-27 Sumitomo Chem Co Ltd 極低温用高純度アルミニウム導体およびその製造方法
JPH083660A (ja) 1994-06-15 1996-01-09 Suzuki Motor Corp Ａｌ基金属間化合物強化複合部をもつ部材と、その製造方法
JPH0841571A (ja) 1994-05-24 1996-02-13 Toyota Central Res & Dev Lab Inc アルミニウム合金およびその製造方法
JPH0881718A (ja) 1994-09-14 1996-03-26 Bernd Dr Kos 軽金属と非金属成分とから成る分散混合物から金属相を取得する方法
JPH09295122A (ja) 1996-05-03 1997-11-18 Japan Steel Works Ltd:The 金属基複合材料の製造方法
JPH11504388A (ja) 1995-05-02 1999-04-20 ザ・ユニバーシティ・オブ・クイーンズランド アルミニウム合金粉末混合物および焼結アルミニウム合金
JP2003181431A (ja) 2001-12-14 2003-07-02 Univ Nagoya 廃棄物処理方法及び廃棄物処理装置
JP2005002331A (ja) 2003-05-21 2005-01-06 Mitsubishi Chemicals Corp 脂肪族ポリエステル及びその製造方法
JP2005248325A (ja) * 2004-02-05 2005-09-15 Topy Ind Ltd マグネシウム複合材料の製造方法
JP2007046122A (ja) * 2005-08-11 2007-02-22 Topy Ind Ltd 圧縮成形体の製造方法
JP2007084876A (ja) 2005-09-22 2007-04-05 Tsutomu Matsuzaki 廃アルミのリサイクル処理方法および処理装置
JP2007084889A (ja) 2005-09-22 2007-04-05 Aisin Seiki Co Ltd アルミニウム合金及びその製造方法
JP2007098243A (ja) 2005-10-03 2007-04-19 Susumu Iketani 金属アルミニウムの回収装置およびアルミドロスのリサイクルシステム
JP2007154246A (ja) 2005-12-02 2007-06-21 Nissei Plastics Ind Co カーボンナノ複合金属成形品の製造方法

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4758273A (en) * 1984-10-23 1988-07-19 Inco Alloys International, Inc. Dispersion strengthened aluminum alloys

Patent Citations (27)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61143531A (ja) * 1984-10-23 1986-07-01 インコ、アロイス、インタ−ナシヨナル、インコ−ポレ−テツド 分散強化アルミニウム合金の改良された製造法
JPS62238344A (ja) 1986-04-04 1987-10-19 インコ、アロイス、インタ−ナシヨナル　インコ−ポレ−テツド 機械的合金化
JPS63211507A (ja) 1987-02-26 1988-09-02 住友電気工業株式会社 音響・画像機器用導体
JPS63241103A (ja) 1987-03-27 1988-10-06 Idea Res:Kk 金属等の粉体固形化方法
JPH04331A (ja) 1990-04-16 1992-01-06 Fujitsu Ltd アルミニウム複合焼結体の製造方法
JPH0574235A (ja) 1991-02-20 1993-03-26 Furukawa Electric Co Ltd:The アルミニウム安定化超電導線
JPH04277605A (ja) 1991-03-06 1992-10-02 Toshiba Corp 超電導々体および超電導コイル
JPH06172891A (ja) 1992-12-07 1994-06-21 Leotec:Kk 複合材の製造方法
JPH06271955A (ja) 1993-01-21 1994-09-27 Toyota Central Res & Dev Lab Inc アルミニウム合金の製造方法
JPH06238422A (ja) 1993-02-19 1994-08-30 Mazda Motor Corp 複合金属部材の製造方法
JPH07166283A (ja) 1993-07-06 1995-06-27 Sumitomo Chem Co Ltd 極低温用高純度アルミニウム導体およびその製造方法
JPH0841571A (ja) 1994-05-24 1996-02-13 Toyota Central Res & Dev Lab Inc アルミニウム合金およびその製造方法
JP3367269B2 (ja) 1994-05-24 2003-01-14 株式会社豊田中央研究所 アルミニウム合金およびその製造方法
JP3417666B2 (ja) 1994-06-15 2003-06-16 スズキ株式会社 Ａｌ基金属間化合物強化複合部をもつ部材と、その製造方法
JPH083660A (ja) 1994-06-15 1996-01-09 Suzuki Motor Corp Ａｌ基金属間化合物強化複合部をもつ部材と、その製造方法
JPH0881718A (ja) 1994-09-14 1996-03-26 Bernd Dr Kos 軽金属と非金属成分とから成る分散混合物から金属相を取得する方法
JPH11504388A (ja) 1995-05-02 1999-04-20 ザ・ユニバーシティ・オブ・クイーンズランド アルミニウム合金粉末混合物および焼結アルミニウム合金
JP3011885B2 (ja) 1996-05-03 2000-02-21 株式会社日本製鋼所 金属基複合材料の製造方法
JPH09295122A (ja) 1996-05-03 1997-11-18 Japan Steel Works Ltd:The 金属基複合材料の製造方法
JP2003181431A (ja) 2001-12-14 2003-07-02 Univ Nagoya 廃棄物処理方法及び廃棄物処理装置
JP2005002331A (ja) 2003-05-21 2005-01-06 Mitsubishi Chemicals Corp 脂肪族ポリエステル及びその製造方法
JP2005248325A (ja) * 2004-02-05 2005-09-15 Topy Ind Ltd マグネシウム複合材料の製造方法
JP2007046122A (ja) * 2005-08-11 2007-02-22 Topy Ind Ltd 圧縮成形体の製造方法
JP2007084876A (ja) 2005-09-22 2007-04-05 Tsutomu Matsuzaki 廃アルミのリサイクル処理方法および処理装置
JP2007084889A (ja) 2005-09-22 2007-04-05 Aisin Seiki Co Ltd アルミニウム合金及びその製造方法
JP2007098243A (ja) 2005-10-03 2007-04-19 Susumu Iketani 金属アルミニウムの回収装置およびアルミドロスのリサイクルシステム
JP2007154246A (ja) 2005-12-02 2007-06-21 Nissei Plastics Ind Co カーボンナノ複合金属成形品の製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
SCRIPTA MATERIALIA, vol. 53, 2005, pages 1225 - 1229

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