EP0568705B1 - Verfahren zum entgasen und erstarren von aluminiumlegierungspulver - Google Patents

Verfahren zum entgasen und erstarren von aluminiumlegierungspulver Download PDF

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Publication number
EP0568705B1
EP0568705B1 EP92923997A EP92923997A EP0568705B1 EP 0568705 B1 EP0568705 B1 EP 0568705B1 EP 92923997 A EP92923997 A EP 92923997A EP 92923997 A EP92923997 A EP 92923997A EP 0568705 B1 EP0568705 B1 EP 0568705B1
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Prior art keywords
powder
temperature
heating
forging
aluminium
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EP92923997A
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English (en)
French (fr)
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EP0568705A1 (de
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 consolidating a rapidly solidified aluminium alloy powder.
  • a number of methods of forming and consolidating a rapidly solidified aluminium alloy powder are known, for example extrusion, HIP and powder forging.
  • HIP high-density polyethylene
  • powder forging In order to consolidate a powder, it is necessary to heat the powder, during which the structure obtained on quenching may be lost with a corresponding to deterioration in the properties. Prevention of such a deterioration is achieved by rapid heating in a short time.
  • a method relating to carrying out rapid heating for the purpose of consolidating a rapidly solidified aluminium alloy powder is disclosed in US Patent No. 4435213; a method relating to induction heating of general powder, not limited to aluminium, is disclosed in US Patent No. 5134260; and a method relating to rapid heating by hot air is disclosed in Japanese Patent Laid-Open Publication No. 158401/1991.
  • heating before consolidation is vital to decrease the deformation resistance of the powder and to allow the powder to be shaped with a low stress and, additionally, for the purpose of degassing.
  • degassing is an indispensable means for preventing the formation of bubbles in a solidified article, known as blistering, and, in the case of powder forging, for forming strong bonds between the grains.
  • degassing is an indispensable means for preventing the formation of bubbles in a solidified article, known as blistering, and, in the case of powder forging, for forming strong bonds between the grains.
  • degassing has generally been carried out by can-sealing a CIP (cold isotactic pressing) body and heating in a vacuum or in an inert gas atmosphere at a temperature of 400 to 600°C.
  • CIP cold isotactic pressing
  • the prior art methods have aimed to effect sufficient degassing by raising the temperature for 0.5 to 2 hours and maintaining it at 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 disadvantage that the structure obtained on quenching, i.e. the effect of precipitating an element or phase finely and uniformly, which tends to be coarsely precipitated at an ordinary cooling rate, or the effect of rendering fine crystal grains, is lost by heating for a long time. This results in a deterioration in the properties of a shaped and consolidated body. Moreover, prevention of oxidation requiring a controlled atmosphere, results in higher productions costs.
  • SU-A-1414501 relates to a method of forming articles from aluminium alloy powders, wherein pressed blanks are heated in an electric furnace to 530°C at 50°C/min.
  • Rapid and uniform heating of a material having a low heat conductivity, such as green compacts, has generally been considered difficult to achieve.
  • the most suitable method for rapid heating on a commercial scale is induction heating.
  • induction heating it has been reported in Japanese Laid-Open Publication No. 134503/1974 that high frequency induction heating may be used for heating and sintering a green compact of a ferrous metal. Up to the present time, such high frequency induction heating has been utilised to effect sintering in a short time or sinter forging (forging for increasing the density of a preform which is being sintered).
  • the present invention provides a method of degassing aluminium powder or an aluminium alloy powder comprising utilising induction heating for a degassing means in a step of forming and consolidating the aluminium powder or aluminium alloy powder, whereby the above described disadvantages of the prior art can be overcome.
  • the present invention provides means for addressing the above described points (A), (B) and (C) and provides a consolidated body having a higher strength and toughness, without a reduction in other mechanical properties, compared with the consolidating methods of the prior art.
  • a consolidating method for obtaining the same in an economical manner is also provided.
  • the inventors have made various studies to solve the above described problems and, consequently, have devised a method whereby degassing of aluminium or aluminium alloy powder can be carried out by the use on induction heating, whilst suppressing a deterioration in the microstructure thereof.
  • the heating time can also 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 aluminium powder, aluminium alloy powder or aluminium composite alloy powder or mixed powders thereof, optionally containing non-metallic grains, before consolidation thereof, characterised 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 a stagnant atmosphere of air at atmospheric pressure, raising the temperature to in the range of from 400 to 600°C at a temperature gradient of at least 0.8°C/sec when a temperature of 300°C has been reached, whereby heat-decomposable volatile components are removed to obtain a hydrogen content of at most 10ppm.
  • the above described induction heating is carried out in air.
  • the present invention consists in preforming aluminium powder, aluminium alloy powder or aluminium composite alloy powder or mixed powders thereof, optionally containing 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 of air at atmospheric pressure, maintaining a temperature-raising gradient of at least 0.8°C/sec when a temperature of 300°C has been reached and raising the temperature to in the range of from 400 to 600°C, corresponding to a temperature of at least 30°C higher than the vacuum degassing temperature applied in the case of extruding the above described powder, whereby heat decomposable volatile components are removed to obtain a hydrogen content of at most 10ppm, and then directly subjecting the thus obtained product to hot working and thus consolidating the product.
  • a higher temperature i.e. 400°C to the melting point
  • an alloy containing only an alloying element Fe, Ni, etc
  • a powder forging method can be used as the above described hot working.
  • the above described induction heating can be carried out in an inexpensive stagnant atmosphere of air and, moreover, both the strength and toughness can be improved compared with the prior art without carrying out degassing in a vacuum before consolidation, without subjecting the material to plastic working, such as extrusion, after consolidation, and without lowering the elongation and fracture toughness.
  • the present invention preferably furthermore comprises 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 preferred 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.
  • Figure 1 is an SEM photograph of a texture of a forged body obtained in Example 2-1) of the present invention.
  • Figure 2 is an SEM photograph of a texture of a forged body obtained in Example 2-3) of the present invention.
  • Figure 3 is an SEM photograph 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 at least 1 hour
  • heating for a long time has ordinarily been carried out using a resistance heating furnace.
  • the microstructure obtained on quenching a powder is lost because the powder is exposed to a high temperature for a long time. Since a H 2 O component in the air hinders the above described H 2 O release reaction, and an O 2 component in the air oxidizes the powder, heating has generally been carried out in a vacuum at a low dew point and low O 2 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 powder particles with each other, and an incident direction of magnetic induction flux of a high frequency and the frequency of the high frequency are optimised.
  • aluminium alloy powder used in the present invention examples include not only rapidly solidified alloy powders but also those prepared by other methods.
  • the composition thereof is not limited, but can be an aluminium composite alloy powder (aluminium or aluminium alloy powder in which a non-metallic or intermetallic compound is dispersed). Aluminium powder can also be used.
  • non-metallic grains such as SiC or Al 2 O 3 grains can be mixed with these powders.
  • aluminium powders, aluminium alloy powders, aluminium composite alloy powders or mixed powders thereof, optionally containing non-metallic grains are 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, a CIP method or other methods, without using heat-decomposable organic lubricants.
  • the powder grains are thus subjected to micro-shearing forces with each other so that they have 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/cm 2 . When this is not accomplished within this pressure range, the mold pressing is carried out at a high pressure or the temperature of the powder is subsequently raised to decrease the deformation resistance thereof.
  • the preform is then subjected directly to induction heating using an electric source and rapidly heated to 400 to 600°C while maintaining a temperature-raising rate of 0.8°C/sec when a temperature of 300°C has been reached, during which the frequency is preferably adjusted to 3 kHz according to the inventors' experiments, although an optimum frequency can suitably be chosen depending on the particular material.
  • An oxide film, i.e. alumina (Al 2 O 3 ), on the surface of the aluminium powder is such a stable compound that it is hardly removed by reduction. This oxide film hinders strong bonding of the aluminium alloy powder grains with each other.
  • a gas-atomised and rapidly solidified aluminium alloy powder has an oxide film with a thickness of 50 to 100 ⁇ covered on the surface thereof, the surface oxide film further containing absorbed water or crystallisation water, which causes a decrease in the elongation or fracture toughness value of the solidified material.
  • a method employed to accelerate these reactions comprises heating for a long time (a longer time allows the reactions to proceed further), heating in a vacuum (a lower atmospheric pressure moves the equilibrium of these reactions to the right) or heating in an inert gas with a low dew point (equilibrium is moved to the right because of less H 2 O (gas) at a low dew point).
  • the object of using the inert gas atmosphere is to prevent the powder from oxidising.
  • the inventors have made various examinations as to methods whereby a sufficient degassing can be carried out in an economical manner even when using rapid heating and, consequently, have found that this problem can be solved by utilising 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 30ppm.
  • the heating temperature should be at least 30°C, preferably at least 50°C, higher than that of the vacuum degassing method 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.
  • 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) consolidation in a short time and (iii) quenching after consolidation.
  • a consolidated 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 the same composition at a higher temperature (substantially the same as the powder forging temperature) because it contains more non-equilibrium phases than those prepared by other methods.
  • N 2 or Ar 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, N 2 or Ar can be detected, while in the consolidated 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/cm 2 .
  • 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/cm 2 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 a 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/cm 2 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/cm 2 .
  • 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/cm 2 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/cm 2 and, after forging, water-cooled.
  • the properties of the products at room temperature were as follows:
  • a gas atomized powder (Al-8.8Fe-3.7Ce) was pressed at a compacting pressure of 4 tons/cm 2 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/cm 2 and after the forging, water-cooled.
  • the properies of the product at room temperature were as follows:
  • a gas atomized powder (Al-8Zn-2.5Mg-1Cu-1.6Co) was pressed at a compacting pressure of 4 tons/cm 2 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/cm 2 .
  • the temperature was lowered to 460°C and the product was reheated to 520 °C in 1 minute by induction heating, water-cooled, then subjected to natural ageing for 4 days, followed by an examination of the properties at room temperature.
  • the same green compact was heated to 510°C for 4 minutes in a nitrogen stream (7 liters/min) and then forged under the same conditions as described above.
  • 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
  • the article of the present invention also has an excellent heat resistance.
  • the tensile strength, elongation and fracture toughness values can be improved without carrying out heating in an inert atmossphere, degassing in vacuum and plastic deformation after consolidation.

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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)

Claims (6)

  1. Verfahren zum Entgasen eines Aluminiumlegierungspulvers bei dem man:
    ein Aluminiumpulver, Aluminiumlegierungspulver oder Aluminiumverbundlegierungspulver oder deren Pulvergemisch, enthaltend wahlweise nichtmetallische Körnchen, vorformt, um einen spezifischen elektrischen Widerstand von höchstens 0,2 Ω cm zu erhalten, wobei der Vorformling in einer stagnierenden Luftatmosphäre bei atmosphärischem Druck direkt induktionserhitzt wird,
    die Temperatur auf einen Wert im Bereich von 400 bis 600°C bei einem Temperaturgradienten von mindestens 0,8°C/sec erhöht, wenn eine Temperatur von 300°C erreicht ist, wodurch die durch Hitze zersetzbaren flüchtigen Komponenten entfernt werden, um einen Wasserstoffgehalt von höchstens 10 ppm zu erhalten.
  2. Verfahren nach Anspruch 1, bei dem die Vorform nach dem Entgasen durch Induktionserhitzen in einer Inertgasatmosphäre gekühlt wird.
  3. Verfahren zum Verfestigen eines rasch erstarrten Aluminiumlegierungspulvers bei dem man:
    ein Aluminiumpulver, Aluminiumlegierungspulver oder Aluminiumverbundlegierungspulver oder deren Pulvergemisch, wahlweise enthaltend nichtmetallische Körnchen, vorformt, um einen spezifischen elektrischen Widerstand von höchstens 0,2 Ω cm zu erhalten, wobei der Vorformling in einer stagnierenden Luftatmosphäre bei atmosphärischem Druck direkt induktionserhitzt wird,
    die Temperatur auf einen Wert im Bereich von 400°C bis zum Schmelzpunkt bei einem Gradienten der Temperaturerhöhung von mindestens 0,8°C/sec erhöht, wenn eine Temperatur von 300°C erreicht ist, wodurch die durch Hitze zersetzbaren flüchtigen Komponenten entfernt werden, um einen Wasserstoffgehalt von höchstens 10 ppm zu erhalten,
    und dann das so erhaltene Produkt direkt heißbearbeitet und verfestigt.
  4. Verfahren nach Anspruch 3, bei dem die Heißbearbeitung durch Pulverschmieden erfolgt.
  5. Verfahren nach Anspruch 3 oder 4, bei dem das Produkt unmittelbar nach dem Schmieden mit einer Geschwindigkeit von mindestens 10°C/sec abgeschreckt oder ohne Abkühlen auf Raumtemperatur bei einer Temperatur von höchstens der Schmiedetemperatur bis zu mindestens der Schmiedetemperatur minus 50°C erneut erhitzt wird.
  6. Verfahren nach einem der Ansprüche 3 bis 5, bei dem das Vorformen des Pulvers durch Beschichten einer Innenwand einer Metallform mit einem Benetzungsmittel ohne Zusatz eines organischen Benetzungsmittels zum Pulver erfolgt.
EP92923997A 1991-11-22 1992-11-20 Verfahren zum entgasen und erstarren von aluminiumlegierungspulver Expired - Lifetime EP0568705B1 (de)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP30787391 1991-11-22
JP307873/91 1991-11-22
JP4769592 1992-02-04
JP47695/92 1992-02-04
PCT/JP1992/001527 WO1993009899A1 (en) 1991-11-22 1992-11-20 Method for degassing and solidifying aluminum alloy powder

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

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

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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
US6346132B1 (en) 1997-09-18 2002-02-12 Daimlerchrysler Ag High-strength, high-damping metal material and method of making the same
DE19741019C2 (de) * 1997-09-18 2000-09-28 Daimler Chrysler Ag Strukturwerkstoff und Verfahren zu dessen Herstellung
JP5492550B2 (ja) * 2009-12-28 2014-05-14 株式会社Ｉｈｉ 脱脂方法
CN110218915B (zh) * 2019-07-05 2021-07-20 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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JPS61281834A (ja) * 1985-06-07 1986-12-12 Sumitomo Electric Ind Ltd アルミニウム合金粉末押出用ビレツトの製造方法
JPS63121628A (ja) * 1986-11-10 1988-05-25 Sumitomo Electric Ind Ltd アルミニウム系粉末合金の製造方法
SU1414501A1 (ru) * 1987-01-12 1988-08-07 Предприятие П/Я Р-6058 Способ изготовлени изделий из порошков алюминиевых сплавов
JPS6475604A (en) * 1987-09-16 1989-03-22 Honda Motor Co Ltd Method for molding aluminum alloy powder
JPH01156402A (ja) * 1987-12-11 1989-06-20 Honda Motor Co Ltd アルミニウム合金の粉末成形法
JPH03281748A (ja) * 1990-03-29 1991-12-12 Sumitomo Light Metal Ind Ltd Ｖｔｒシリンダー材の製造方法

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KR930703101A (ko) 1993-11-29
EP0568705A1 (de) 1993-11-10
EP0568705A4 (en) 1995-11-29
DE69225469D1 (de) 1998-06-18
WO1993009899A1 (en) 1993-05-27
JP3336645B2 (ja) 2002-10-21
JPH05320709A (ja) 1993-12-03
KR960007499B1 (ko) 1996-06-05
DE69225469T2 (de) 1998-09-24

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