EP0568705A1 - Procede pour degazer et solidifier des poudres d'alliage d'aluminium - Google Patents

Procede pour degazer et solidifier des poudres d'alliage d'aluminium Download PDF

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Publication number
EP0568705A1
EP0568705A1 EP92923997A EP92923997A EP0568705A1 EP 0568705 A1 EP0568705 A1 EP 0568705A1 EP 92923997 A EP92923997 A EP 92923997A EP 92923997 A EP92923997 A EP 92923997A EP 0568705 A1 EP0568705 A1 EP 0568705A1
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Prior art keywords
powder
temperature
alloy powder
aluminum alloy
heating
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EP92923997A
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German (de)
English (en)
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EP0568705B1 (fr
EP0568705A4 (en
Inventor
T. Itami Works Of Sumitomo El. Ind. Ltd. Kaji
Y. Itami Works Of Sumitomo El. Ind. Ltd Takeda
Y. Itami Works Of Sumitomo El. Ind. Ltd Odani
K. Itami Works Of Sumitomo El. Ind. Ltd Akechi
T. Itami Works Of Sumitomo El. Ind. Ltd. Tanji
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Sumitomo Electric Industries Ltd
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Sumitomo Electric Industries Ltd
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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
    • B22F3/10—Sintering only
    • B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
    • 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
    • B22F1/12—Metallic powder containing non-metallic particles
    • 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
    • B22F1/14—Treatment of metallic powder
    • B22F1/142—Thermal or thermo-mechanical treatment
    • 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
    • B22F3/02—Compacting only
    • 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
    • B22F3/10—Sintering only
    • B22F3/1017—Multiple heating or additional steps
    • 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
    • B22F3/10—Sintering only
    • B22F3/1017—Multiple heating or additional steps
    • B22F3/1028—Controlled cooling
    • 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
    • B22F3/24—After-treatment of workpieces or articles

Definitions

  • This invention relates to a method of degassing and solidifying a rapidly solidified aluminum alloy powder.
  • 5134260 "Method and Apparatus for Inductively Heating Powders or Powder Compacts for Consolidation; Carnegie Melon University” and a patented invention relating to rapidly heating by hot air is 3 Japanese Patent Laid-Open Publication No. 158401/1991: "Method of Heating Rapidly Solidified Powders; Kubota”.
  • the degassing is an indispensable means for preventing a solidified article from forming of bubbles called blistering and in the case of the powder forging, strongly bonding grains with each other, for example, like known methods described in Japanese Patent Laid-Open Publication No. 224602/1987 and "Kei-Kinzoku (Light Metals)" 37 (10) 1987, page 656-664.
  • degassing has generally been carried out by can-sealing a CIP (cold isotactic pressing) body and heating in vacuum or in an inert gas atmosphere at a temperature of 400 to 600 °C .
  • CIP cold isotactic pressing
  • Any prior art method has aimed at completing sufficiently degassing by raising the temperature for 0.5 to 2 hours and maintianing a predetermined temperature for 0.5 to 2 hours, amounting to 1 to 4 hours, using an ordinary resistance heating furnace.
  • the above described degassing method has the disadvantages that the quenching effect of a powder, i.e. the effect of precipitating finely and unifromly an element or phase which tends to be coarsely precipitated at an ordinary cooling rate or the effect of rendering crystal grains fine is lost by heating for a long time to deteriorate the properties of a shaped and solidified body, and moreover, prevention of oxidation during then needs controlling of the atmosphere, resulting in rising of the production cost.
  • the inductive heating has not been used for degassing of a green compact of aluminum powder or aluminum alloy powder.
  • the reasons therefor are as follows: It has been considered that the presence of a stable alumina film (Al2O3 ) with a low electric conductivity on surfaces of aluminum powder or aluminum alloy powder results in increase of the resistance of the powder and decrease of the electric conductivity of a green compact and an effective heating is impossible by induction heating since Joule's heat is hard to be generated in a material with a low electric conductivity, such as aluminum, eddy current is hard to be generated in the green compact and aluminum itself has a smaller magnetic permeability different from ferruginous materials.
  • the present invention provides a method of degassing aluminum powder or an aluminum alloy powder comprising utilizing induction heating for a degassing means in a step of forming and solidifying the aluminum powder or aluminum alloy powder, whereby the above described disadvantages of the prior art can be overocme.
  • the rapid heating method by the induction heating or hot air heating method as disclosed in the foregoing three patents is favourable.
  • the rapid heating method there arises a problem that the bonding of aluminum powder with each other [subject (B)] is hard to take place. Therefore, the heating in the air, as described in Example of the patent 1 , results in lowering of the fracture elongation even if the extrusion is carried out.
  • the present invention provides means for solving the above described subjects (A), (B) and (C) and provides a soldified body having a higher strength and toughness without lowering mechanical properties as compared with any of solidifying methods of the prior art and a solidifying method for obtaining the same in economical manner.
  • the inventors have made various studies to solve the above described problems and consequently, have found a method whereby degassing of aluminum or aluminum alloy powder can be carried out with suppressing deterioration thereof by the use of induction heating and the heating time can be decreased to about 1/10 of the prior art.
  • the present invention is based on this finding.
  • the present invention provides a method of degassing aluminum powder, aluminum alloy powder or aluminum composite alloy powder or mixed powders thereof with non-metallic grains, before solidification thereof, characterized by preforming the powder body to give a specific electric resistance of at most 0.2 ⁇ cm, subjecting the preform directly to induction heating in an atmosphere at normal pressure, temperature-raising to 400 to 600°C at a temperature gradient of at least 0.4 °C/sec in a temperature range of at least 300 °C, and removing heat-decomposable volatile components to obtain a hydrogen content of at most 10 ppm.
  • the above described induction heating can be carried out in the atmosphere.
  • the feature of the present invention consists in preforming aluminum powder, aluminum alloy powder or aluminum composite alloy powder or mixed powders thereof with non-metallic grains to give a specific electric resistance of at most 0.2 ⁇ cm, subjecting the preform directly to induction heating in a stagnant atmosphere at normal pressure, maintaining a temperature-raising gradient of at least 0.4 °C/sec at a temperature range of at least 300 °C, temperature-raising to 400 to 600 °C corresponding to a temperature of at least 30 °C higher than the vacuum degassing temperature applied to a case of extruding the above described powder, removing heat-decomposable volatile components to obtain a hydrogen content of at most 10 ppm, then directly subjecting a product to hot working and thus solidifying the product.
  • a higher temperature i.e. 400 °C to the melting point can be chosen in the case of an alloy containing only an alloying element (Fe, Ni, etc.) which does not lower the melting point of Al (MP 660 °C ).
  • a powder forging method can be used as the above described hot working.
  • the above described induction heating can be carried out in the inexpensive stagnant atmosphere and moreover, both the strength and toughness can more be improved than in the prior art without degassing in vacuum before solidifying, without subjecting to plastic working such as extrusion after solidifying and without lowering the elongation and fracture toughness.
  • the feature of the present invention consists in quenching at a rate of at least 10 °C immediately after forging, or reheating at a temperature of at most the forging temperature and at least (the forging temperature - 50 °C ) without cooling to room temperature and subjecting to a quenching and solution treatment.
  • a particularly preferable embodiment of the present invention comprises carrying out the preforming of the above described powder after coating the inner wall of a metallic mold with a wetting agent without adding an organic wetting agent to the powder.
  • Infrared radiation heating or direct electric heating can also be used instead of the above described induction heating.
  • Fig. 1 is an SEM photograph instead of a drawing of a texture of a forged body obtained in Example 2-1) of the present invention.
  • Fig. 2 is an SEM photograph instead of a drawing of a texture of a forged body obtained in Example 2-3) of the present invention.
  • Fig. 3 is an SEM photograph instead of a drawing of a texture of a forged body obtained in Comparative Example 2-6) of the present invention.
  • heating for a long time e.g. at least 1 hour has ordinarily been carried out using a resistance heating furnace up to the present time, but the quenching effect of a powder is lost because of being exposed to the high temperature for a long time, as described above.
  • H2O component in the air hinders the above dscribed H2O release reaction and O2 component in the air oxidizes the powder, moreover, the heating has generally been carried out in vacuum, in a low dew point and low O2 concentration atmosphere or in an inert gas atmosphere so as to prevent this phenomenon.
  • the above described conditions are that the compacting pressure of a pressing mold is increased by about 20 % as large as the prior art so as to increase electric contact of a powder with each other, and an incident direction of magnetic induction flux of a high frequency and the frequency of the high frequecncy are selected to be optimum.
  • Examples of the aluminum alloy powder used in the present invention include not only the rapidly solidified alloy powders but also those prepared by any other methods.
  • the composition thereof is not limited, but can be an aluminum composite alloy powder (aluminum or aluminum alloy powder in which a non-metallic or intermetallic compound is dispersed). Aluminum powder can also be used.
  • non-metallic grains such as SiC or Al2O3 grains can be mixed with these powders.
  • aluminum powder, aluminum alloy powders, aluminum composite alloy powders or mixed powders thereof with non-metallic grains are respectively formed into a preform with an increased density to give a specific electric resistance of at most 0.2 ⁇ cm.
  • the forming in this case can be carried out by a mold pressing method such as uniaxial compression method, a CIP method or other methods, without using heat-decomposable organic lubricants.
  • the powder grains are thus subject to micro-shearing forces with each other so that they ha ve metallic contact areas with each other.
  • the specific electric resistance of at most 0.2 ⁇ cm can generally be accomplished by a compacting pressure of 4 to 6 tons/cm2. When this is not accomplished within this range, the mold pressing is carried out at a high pressure or after the temperature of the powder is raised to decrease a deformation resistance thereof.
  • the preform is then subjected directly to induction heating using an electric source and rapidly heated at 400 to 600 °C while maintaining a temperature-raising rate of 0.4 °C/sec at a temperature of at least 300 °C, during which the frequency is preferably adjusted to 3 kHz according to the inventor's experiment, although an optimum frequency can suitably be chosen depending on a subject to be heated.
  • the interior state mainly governs a tensile strength and hardness, so if the thermal history for solidification is reduced, the tensile strength and hardness of the powder itself are naturally increased.
  • properties such as fracture elongation and fracture toughness are mainly governed by the surface state of the rapidly solidified powder.
  • An oxide film, i.e. alumina (Al2O3) on the surface of the aluminum powder is such a stable compound that is hardly removed by reduction. This oxide film hinders strong bonding of the aluminum alloy powder grains with each other. Accordingly, there has been proposed a method comprising subjecting the powder to a plastic flow working, e.g. extrusion or upset working, thus meachanically breaking the oxide film, exposing and bonding fresh surfaces of aluminum. It has been known up to the present time, however, that even when using the extrusion method, there is obtained only a product with a low elongation and low fracture toughnes value if degassing before the solidification is insufficient.
  • a plastic flow working e.g. extrusion or upset working
  • a gas-atomized and rapidly solified aluminum alloy powder has an oxide film with a thickness of 50 to 100 ⁇ covered on the surface thereof, the surface oxide film further containing adsorbed water or crystallization water, which causes lowering of the elongation or fracture toughness value of the solidified material.
  • a method having been employed to accelerate these reactions comprises heating for a long time (longer time allows to proceed more reactions), heating in vacuum (lower atmospheric pressure results in tendency of proceeding of these reactions to right) or heating in an inert gas with a low dew point (these reactions tend to proceed to right because of less H2O (gas) at a low dew point).
  • the object of using the inert gas atmosphere is to prevent the powder from oxidation.
  • the inventors have made various examinations as to methods whereby a sufficient degassing can be carried out in economical manner even when using a rapid heating and consequently, have found that this problem can be solved by utilizing the hydrogen gas evolved by the above described release reaction.
  • the above described generation of hydrogen gas takes place, in particular, at a high temperature.
  • the amount of the thus generated hydrogen gas is generally about 30 ppm.
  • the heating at a temperature of at least 300 °C for generating hydrogen should be carried out at a rate of at least 0.4 °C/sec, and in order to generate hydrogen in a large amount in a series of the degassing reactions, it is required to heat up to a temperature of as higher as possible.
  • the heating temperature should be a temperature of at least 30 °C, preferably at least 50 °C higher than that of the vacuum degassing carried out before extrusion in the prior art (generally heated at about 450 °C ). In this way, the structure of the powder surface tends to be fixedly bonded. As a measure of the tendency of bonding of the powder, it is required that that the amount of the residual hydrogen is at most 10 ppm.
  • the structure of the interior part of the powder tends to be coarse even if rapid heating is effected and it is required to carry out (i) heating in a short time, (ii) solidifying in a short time and (iii) quenching after solidifying.
  • a solidified body according to the present invention has a feature such as to be more changeable (concerning the structure distribution of a precipitate, obtained by X-ray diffraction, shape of a precipitate, size of a precipitate -tendency of coarsening-) for a same composition at a high temperature (substantially same as the powder forging temperature) because of containing more non-equilibrium phases, than those prepared by other methods.
  • N2 or Ar element When a powder is heated for a long time in an inert gas and then subjected to extrusion or powder forging so as to turn out the air (predominantly consisting of nitrogen) contained in pores or gaps by hydrogen released from the powder surface, N2 or Ar element can be detected, while in the solidified body of the present invention, such elements are contained only in an amount of at most the detectable limit.
  • the degassed powder obtained according to the present invention having such a clean surface as having little adsorbed water or crystalline water, can be subjected to powder forging as heated. Accordingly, this is forged by a known forging method just after degassing.
  • an induction heating has the disadvantage that the temperature of a body to be heated is more non-uniform as compared with an ordinary atmospheric heating furnace and accordingly, when the temperature gradient is large, the temperature thereof can be rendered uniform by holding at a predetermined temperature in an atmospheric heating furnace after temperature raising, during which the atmosphere should be of an inert gas.
  • the preform rapidly heated and degassed in this way is immediately charged in a metallic mold at about 200 °C and subjected to forging at a compacting pressure of 2 to 12 tons/cm2.
  • the temperature-raising efficiency is not good at a specific electric resistance of about 0.2 ⁇ cm or more.
  • An air-atomized powder (mean grain diameter: about 50 ⁇ m) with a composition of Al-25Si-2.5Cu-1Mg (by weight, same hereinafter) was compacted in a diameter 100 mm x height 20 mm to give a specific electric resistance of 0.02 ⁇ cm and heated in the air to 500 °C from room temperature for 4 minutes by induction heating.
  • the product was immediately charged in a metallic mold (200 °C ) lined with graphite lubricant, powder-forged at a compacting pressure of 8 tons/cm2 and just after the forging, cooled by immersing in water at room temperature.
  • the foreged body was subjected to natural ageing for 4 days, after which Rockwell hardness B scale (H R B) was measured to obtain an H R B of 86.
  • H R B Rockwell hardness B scale
  • Example 1 For comparison, the green compact prepared in the similar manner to Example 1 was heated for 1 hour in a nitrogen atmosphere at 500°C in a resistance furnace and after heating, forged, cooled and then subjected to natural ageing and measurement of the hardness to obtain an H R B of 79 (ComparativeExample 1).
  • the green compact was exposed to an atmosphere at a temperature of 40 °C and a humidity of 90 % for 24 hours, before heating and degassing, thus adsorbing a large amount of water on the surface of the powder, and then subjected to the steps after the heating and degassing in the similar manner.
  • Example 2-1) and 2-4) and Comparrative Examples 2-6) and 2-7) were repeated except using a mixed powder of air-atomized, Al-20Si-5Fe-2Ni alloy powder (mean grain diameter: 50 ⁇ m ) and alumina powder with a mean grain diameter of 0.5 ⁇ m, as a raw material powder, thus obtaining forged bodies 3-1) and 3-2) of the present invention and comparative articles 3-3) and 3-4).
  • the properties measured in the similar manner to Example 2 are shown in Table 6.
  • the quantity of oxygen is a quantity from which the quantity of oxygen contained in the alumina grains has been removed by calculation.
  • An atomized powder with a composition of Al-25Si-2.5Cu-1Mg (by weight %) was formed in a shape of ⁇ 50 mm x 50 mm t under a pressure of 4 tons/cm2 by a die wall lubricating mold, heated to a forging temperature for 4 minutes by induction heating and forged in a shape of ⁇ 53 mm.
  • the forging conditions were a heating temperature of 500 °C and a forging pressure of 5 tons/cm2.
  • the product was subjected to a T6 heat treatment (comprising holding at 490 °C for 1.5 hours, immersing in water and subjecting to an ageing treatment at 180 °C for 6 hours) and subjected to estimation of the strength.
  • a gas atomized powder (Al-7.3Ni-2.9Fe) was pressed at a compacting pressure of 4 tons/cm2 to prepare three samples each having a shape of ⁇ 70 mm x 25 mmt, heated to 550 °C for 2 minutes by induction heating for one sample, by radiation heating for another sample and by direct electric heating for a further sample, and then forged in ⁇ 72 mm at a forging pressure of 8 tons/cm2 and after the forging, water-cooled.
  • the properties of the products at room temperature were as follows: Induction-heated product: tensile strength 62.3 kg/mm2, elongation 13.5 %, K IC 28.0 kg/mm2 ⁇ m Radiation-heated product: tensile strength 60.1 kg/mm2, elongation 13.0 %, Direct elctrically-heated product: tensile strength 63.4 kg/mm2, elongation 13.6 %
  • a gas atomized powder (Al-8.8Fe-3.7Ce) was pressed at a compacting pressure of 4 tons/cm2 to prepare a samples having a shape of ⁇ 70 mm x 25 mm t, induction-heated to 550°C for 1.5 minutes and then forged in ⁇ 72 mm at a forging compacting pressure of 8 tons/cm2 and after the forging, water-cooled.
  • the properies of the product at room temperature wasas follows: Tensile strength: 65.2 kg/mm2 and elongation: 16.2 %
  • a gas atomized powder (Al-8Zn-2.5Mg-1Cu-1.6Co) was pressed at a compacting pressure of 4 tons/cm2 to prepare a sample having a shape of ⁇ 70 mm x 25 mm t, induction-heated to 530 °C for 1 minute and then forged in ⁇ 72 mm at a forging pressure of 8 tons/cm2. After the forging, the temperature was lowered to 460°C and accordingly, the product was reheated to 520 °C in 1 minute by induction heating, water-cooled and subjected to natural ageing for 4 days, followed by examining the properties at room temperature.
  • the product was induction-heated to 485 °C for 1 minute, water-cooled and subjected to an ageing treatment of 175 °C x 6 hours to obtain a rapidly reheated T6 material.
  • the product was charged in a furnace at 485 °C for 10 minutes, water-cooled and subjected to an ageing treatment of 175°C x 6 hours to obtain a reheated T6 material.
  • the product was directly water-cooled and then subjected to a T6 treatment (i.e. subjected to 485 °C x 2 hours, water-cooling and a treatment of 175 °C x 6 hours) to obtain a T6 material.
  • a T6 treatment i.e. subjected to 485 °C x 2 hours, water-cooling and a treatment of 175 °C x 6 hours

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  • Engineering & Computer Science (AREA)
  • Manufacturing & Machinery (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Optics & Photonics (AREA)
  • Powder Metallurgy (AREA)
  • Extrusion Of Metal (AREA)

Abstract

L'invention se rapporte à un procédé pour dégazer et solidifier des poudres d'alliage d'aluminium, qui permet d'éliminer les inconvénients inhérents à la méthode classique, en rendant le chauffage par induction disponible pour les organes de dégazage pendant les processus de formation et de solidification de la poudre d'aluminium et de la poudre d'alliage d'aluminium. Ce procédé consiste à préformer une poudre d'aluminium, une poudre d'alliage d'aluminium et une poudre d'alliage composite d'aluminium ou des mélanges pulvérulents de ces poudres et de particules métalliques non ferreuses à une résistance spécifique égale ou inférieure à 0,2 OMEGA cm, à retirer les constituants d'évaporation décomposables par voie thermique en procédant directement au chauffage par induction du corps préformé dans l'atmosphère à pression normale, pour en accroître la température à un niveau compris entre 400 °C et 600 °C, tout en maintenant un gradient de hausse de température au-dessus de 300 °C à 0,4 °C/scm ou plus, et à réduire la teneur en hydrogène à un niveau inférieur à 10 ppm.
EP92923997A 1991-11-22 1992-11-20 Procede pour degazer et solidifier des poudres d'alliage d'aluminium Expired - Lifetime EP0568705B1 (fr)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP307873/91 1991-11-22
JP30787391 1991-11-22
JP4769592 1992-02-04
JP47695/92 1992-02-04
PCT/JP1992/001527 WO1993009899A1 (fr) 1991-11-22 1992-11-20 Procede pour degazer et solidifier des poudres d'alliage d'aluminium

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EP0568705A1 true EP0568705A1 (fr) 1993-11-10
EP0568705A4 EP0568705A4 (en) 1995-11-29
EP0568705B1 EP0568705B1 (fr) 1998-05-13

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EP (1) EP0568705B1 (fr)
JP (1) JP3336645B2 (fr)
KR (1) KR960007499B1 (fr)
DE (1) DE69225469T2 (fr)
WO (1) WO1993009899A1 (fr)

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FR2768436A1 (fr) * 1997-09-18 1999-03-19 Daimler Benz Ag Materiau offrant un bon amortissement materiel et une bonne resistance a la traction, et procede de fabrication de ce materiau
US6346132B1 (en) 1997-09-18 2002-02-12 Daimlerchrysler Ag High-strength, high-damping metal material and method of making the same
CN110218915A (zh) * 2019-07-05 2019-09-10 江苏豪然喷射成形合金有限公司 一种AlSi20Fe5Ni2坯料的制备方法

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JP2749761B2 (ja) * 1993-08-09 1998-05-13 本田技研工業株式会社 高耐力・高靭性アルミニウム合金粉末の粉末鍛造方法
JP5492550B2 (ja) * 2009-12-28 2014-05-14 株式会社Ｉｈｉ 脱脂方法

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FR2768436A1 (fr) * 1997-09-18 1999-03-19 Daimler Benz Ag Materiau offrant un bon amortissement materiel et une bonne resistance a la traction, et procede de fabrication de ce materiau
US6346132B1 (en) 1997-09-18 2002-02-12 Daimlerchrysler Ag High-strength, high-damping metal material and method of making the same
CN110218915A (zh) * 2019-07-05 2019-09-10 江苏豪然喷射成形合金有限公司 一种AlSi20Fe5Ni2坯料的制备方法

Also Published As

Publication number Publication date
EP0568705B1 (fr) 1998-05-13
WO1993009899A1 (fr) 1993-05-27
DE69225469D1 (de) 1998-06-18
EP0568705A4 (en) 1995-11-29
KR930703101A (ko) 1993-11-29
JP3336645B2 (ja) 2002-10-21
JPH05320709A (ja) 1993-12-03
DE69225469T2 (de) 1998-09-24
KR960007499B1 (ko) 1996-06-05

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