EP2799165B1 - Verfahren zum formen eines aluminiumlegierungspulvers und aluminiumlegierungsteil - Google Patents

Verfahren zum formen eines aluminiumlegierungspulvers und aluminiumlegierungsteil Download PDF

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Publication number
EP2799165B1
EP2799165B1 EP13800173.0A EP13800173A EP2799165B1 EP 2799165 B1 EP2799165 B1 EP 2799165B1 EP 13800173 A EP13800173 A EP 13800173A EP 2799165 B1 EP2799165 B1 EP 2799165B1
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Prior art keywords
aluminum alloy
forming
temperature
sparsely
alloy powder
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EP13800173.0A
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English (en)
French (fr)
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EP2799165A1 (de
EP2799165A4 (de
Inventor
Hideaki Matsuoka
Mikio Kondoh
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Toyota Central R&D Labs Inc
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Toyota Central R&D Labs Inc
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    • 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
    • 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
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their 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
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy

Definitions

  • the present invention relates to an aluminum alloy member comprising a formed body obtained through compression forming of an aluminum alloy powder, and also to a method for forming an aluminum alloy powder suitable therefor.
  • US 5,372,775 discloses a method of preparing an aluminum matrix particle composite alloy containing dispersed ceramic particles, the method comprising the following steps: (a) providing a molten metal of an aluminum alloy, containing said ceramic particles, (b) disintegrating, by atomization, said aluminum alloy molten metal containing said ceramic particles to prepare a powder of composite grains containing said particles being not more than 20 ⁇ m in mean particle diameter, and (c) warm-forming and solidifying said powder of composite grains without melting said composite grains, by powder forging said powder by annealing said powder at a temperature in a range between 200 °C and 450 °C, cold compression-molding said annealed powder to form an initial compact having a true density ratio of at least 70 percent, and warm-molding and compacting said initial compact at a temperature in a range between 400 °C and 550 °C to form a final compact having a true density ratio of at least 99 percent.
  • the powder-metallurgical methods described in the above PTL are all such that the aluminum alloy powder is compressively molded to form a compressed powder body (or preform) and the compressed powder body thus obtained is heated to a high temperature which is not lower than a solidus temperature determined depending at least on the alloy composition.
  • all of the above conventional powder-metallurgical methods are liquid-phase sintering methods in which liquid phases are formed at the surfaces (or interfaces) of powder particles so that the powder particles are bonded to one another.
  • the compressed powder body may be held under a high temperature environment for a long period of time. Therefore, even though the powder particles constituting the compressed powder body originally had a rapidly-solidified fine structure, the fine structure may not be maintained, and the high properties possessed intrinsically by the powder particles may not be effectively exploited.
  • an abnormal structure may be made such that a molten portion caused at the time of sintering is re-solidified, and this abnormal structure may appear locally between the powder particles (at the interface between the particles). This may result in an inhomogeneous structure of the liquid-phase sintered body, and the characteristics thus tend to fluctuate.
  • the composition of aluminum alloy powder to be used may be limited; the structure of the obtained sintered body tends to be inhomogeneous; and heating may be necessary at a high temperature for a long period of time. It may thus be difficult to produce an aluminum alloy member of high properties at low cost.
  • the sintering method itself generally includes, in addition to the liquid-phase sintering method, a solid-phase sintering method in which solid-phase diffusion is caused between contacting powder particles so that the powder particles are bonded to one another.
  • a solid-phase sintering method in which solid-phase diffusion is caused between contacting powder particles so that the powder particles are bonded to one another.
  • the surfaces of powder particles of aluminum alloy are covered by oxide films which are significantly stable and strong up to a high temperature. Therefore, when aluminum alloy powder is used, it may actually be impossible to sinter the powder particles with one another in solid-phase without causing liquid phases at the surfaces of the powder particles (i.e., at a lower temperature than the solidus temperature).
  • liquid-phase sintering may simply be referred to as "sintering" in the present description unless otherwise stated.
  • the section of the scope of claim(s) in the above PTL 2 includes a recitation that a formed body is obtained by performing compression forming of a preform "at a temperature that is not higher than a temperature at which sintering does not start.”
  • a preform is heated to 500 degrees C, for example, and the preform comprises an aluminum alloy powder having an alloy composition of Al-19.5%Si-5.3%Fe-4.9%Cu-1.2%Mg-0.3%Mn (wt%) (First Example).
  • the solidus temperature of an aluminum alloy having that alloy composition may be about 490 degrees C in an equilibrium state. If so, the recitation in the scope of claim(s) of PTL 2 appears to conflict with the description of Examples, and the preform may actually be heated at a temperature at which a liquid phase occurs in the preform or the formed body. This can be found from the fact that some dimensional change occurs in the preform of 500 degrees C described in the section of Examples in PTL 2 (Second Table). Therefore, it may be apparent that the "formed body" referred to in PTL 2 is actually a liquid-phase sintered body in which a liquid phase caused between the powder particles is re-solidified so that the powder particles are bonded one another. In the first place, PTL 2 is not to avoid the occurrence of liquid-phase sintering, and aims to suppress the coarsening of primary crystals Si included in the aluminum alloy powder particles.
  • the present invention has been created in view of such circumstances, and an object of the present invention is to provide a method for forming an aluminum alloy powder in which, unlike in the conventional liquid-phase sintering method or the like, the powder particles can be bonded (fixed) to one another in a solid phase state. Another object of the present invention is to provide an aluminum alloy member obtained therethrough.
  • the present inventors have successfully obtained a formed body by forming an aluminum alloy powder at two different levels of pressures (or density ratios).
  • the powder particles are metallically bonded to one another without causing a liquid phase between the powder particles (solid-phase bonding).
  • the present invention has been accomplished as will be described hereinafter.
  • the sparsely compact material obtained in the compacting step according to the present invention is such that the aluminum alloy powder is pressurized to be formed under a relatively low first pressure (P1).
  • P1 first pressure
  • This sparsely compact material maintains its certain shape so that the powder particles (microparticles) of aluminum alloy are intertangled by plastic deformation, but in this state the microparticles merely abut and engage with one another via surface oxidation films, and a lot of spaces (gaps) remain between the microparticles.
  • Such microparticles are still sufficiently allowed to cause relative displacement and/or plastic deformation due to external force applied.
  • the sparsely compact material comprising the microparticles in such a state is heated to a temperature not higher than the solidus temperature or to a temperature of 300 to 480 degrees C, and the second pressure (P2) higher than the above first pressure (P1) is applied in the forming step according to the present invention, the microparticles constituting the sparsely compact material may further be deformed to plastically flow. At this time, relative displacement may occur between the surfaces of the contacting microparticles (at the interface between the contacting microparticles), so that the thin oxidation films existing on the surfaces of the microparticles may be destroyed by physical (or mechanical) external force.
  • the phenomenon as described above can be utilized for various aluminum alloy powders because the phenomenon does not depend on the alloy composition of the microparticles and need not high temperature heating beyond the solidus temperature or the like. Therefore, it is possible to effectively take advantage of the rapidly-solidified structure originally possessed by the aluminum alloy powder. Moreover, it is not necessary to give a considerably large deformation as in an extrusion process and the like, and it may be enough if the second pressure is applied to the sparsely compact material to such an extent that the surface oxidation films on the microparticles can be destroyed. Thus, according to the forming method of the present invention, even in a case of a formed body (aluminum alloy member) having high properties and a complex shape, the formed body can be efficiently produced at low cost.
  • the present invention can be perceived not only as the above described forming method but as an aluminum alloy member. That is, the present invention can be understood as an aluminum alloy member characterized by comprising the formed body obtained through the above method for forming an aluminum alloy powder.
  • the present invention will be described in more detail with reference to embodiments of the invention.
  • the content described herein may cover not only a method for forming an aluminum alloy powder but an aluminum alloy member obtained therethrough.
  • Features regarding a manufacturing method when understood as a product-by-process claim, may also be features regarding a product.
  • One or more features freely selected from the description herein may be added to the above-described features of the present invention. Which embodiment is the best or not may be different in accordance with objectives, required performance and other factors.
  • the compacting step is a step that applies a first pressure (P1) to an aluminum alloy powder to obtain a sparsely compact material (preform) in which spaces remain.
  • P1 first pressure
  • preform sparsely compact material
  • the forming step is a step that applies a second pressure (P2) to the sparsely compact material to obtain a formed body in which the microparticles constituting the sparsely compact material are metallically bonded to one another.
  • P2 second pressure
  • the aluminum alloy powder comprising the following alloy composition according to the present invention there can be obtained a formed body and an aluminum alloy Kabushiki Kaisha Toyota Chuo Kenkyusho member which are excellent not only in the strength and the ductility but also in the heat resistance, even without performing a heat treatment.
  • the aluminum alloy according to the present invention has an alloy composition comprising, when whole thereof is assumed to be 100 mass% (referred simply to as "%", hereinafter), iron (Fe): 2-7%, zirconium (Zr): 0.6-1.5%, titanium (Ti): 0.5-1%, and optionally magnesium (Mg): 0.5-2.2%, and modifying elements including Cr, Mn, Co, Ni, Sc, Y, Ca, V, Hf and Nb, the balance being aluminum (Al) and inevitable impurities.
  • % mass%
  • iron (Fe) 2-7%
  • zirconium (Zr) zirconium
  • Ti titanium
  • Mg magnesium
  • modifying elements including Cr, Mn, Co, Ni, Sc, Y, Ca, V, Hf and Nb, the balance being aluminum (Al) and inevitable impurities.
  • first compound phase an intermetallic compound
  • Al-Fe-based intermetallic compound Al-Fe-based intermetallic compound
  • This first compound phase enhances the strength and/or hardness of the aluminum alloy.
  • this first compound phase may not necessarily be thermally stable, and phase transformation and/or shape variation (coarsening), etc. may occur if the first compound phase is exposed to a high temperature atmosphere for long time.
  • an appropriate amount of Zr and Ti cooperates with Al to form an Al-(Zr, Ti)-based intermetallic compound (second compound phase) of L1 2 -type structure.
  • This intermetallic compound may be formed in the mother phase such that Zr and Ti having formed supersaturated solid solution in the mother phase precipitate in an ultrafine form (e.g., average size is about 1 to 30 nm) such as when the aluminum alloy is heated.
  • the second compound phase which is a commensurate phase that is commensurate with the mother phase, may appear in the vicinity of a boundary (interface) between the Al-Fe-based intermetallic compound and the mother phase and may be stable up to a high temperature range. Accordingly, the second compound phase is unlikely to cause phase transformation and/or coarsening at least at a temperature not higher than the temperature at which the precipitation starts.
  • the first compound phase may be responsible for the strength and/or hardness of the aluminum alloy
  • the second compound phase which is present in the vicinity of a site at which the first compound phase is in contact with the mother phase, may operate to suppress the phase transformation and/or shape variation (performs so-called pinning operation) at the time of high temperature.
  • the properties such as strength exhibited by the first compound phase can be maintained up to a high temperature range by the second compound phase. It is thus considered that the first compound phase and the second compound phase operate synergistically thereby to allow the aluminum alloy member or the like comprising the above alloy composition to exhibit excellent heat resistance, which would not be expected by the conventional technique.
  • the second compound phase has a nanoparticle-like shape in which the concentration of Zr is high at the central part while the concentration of Ti is high at the outer part.
  • each concentration of Zr and Ti in Al 3 (Zr, Ti) has a gradient from the central part to the outer part. It is important for the formation of the second compound phase that Zr exists much more than Ti and the mass ratio of Zr to Ti (Zr/Ti) is within a predetermined range.
  • the second compound phase in order for the second compound phase to be finely dispersed in the mother phase in the vicinity of the boundary with the first compound phase, it is also important that Zr and Ti form sufficient solid solution (supersaturated solid solution) and are precipitated afterward. Specifically, it may be necessary that, after rapid solidification is conducted to cause an appropriate amount of Zr and Ti to form supersaturated solid solution, some energy is imparted to generate a driving force for facilitating the precipitation. Examples of such energy include thermal energy applied such as by heat treatment and hot working, and strain energy applied such as by plastic working. For example, according to the forming step in the present invention, thermal energy and strain energy can be applied at the same time to accelerate the precipitation of the second compound phase, and there can thus be efficiently obtained a formed body or the like comprising the heat resistant, high strength aluminum alloy.
  • atomizing method or the like may be employed to obtain aluminum alloy powder comprising particles in a state in which Zr and Ti form supersaturated solid state in an Al base.
  • molten alloy comprising the above-described alloy composition may be rapidly solidified at a cooling rate not less than 300 degrees C per second.
  • the second compound phases may also be precipitated using some heat treatment (e.g., aging treatment) and the like.
  • the aluminum alloy member comprising the formed body according to the present invention is not limited in its use application or the like, but may be suitable for members, such as a member having a complex shape, for which high properties (such as mechanical property and heat resistance) are required.
  • members include high strength members, such as a piston, inlet valve and con rod of an internal-combustion engine; a rotor (impeller) of a supercharger; a bladed wheel and piston of a compressor; screws; and an underbody component, shift fork and synchronizer ring of a car, which have been manufactured such as by forge processing and metallic forming casting and which have complex shapes and are to be used under an environment of high temperature or high load.
  • the aluminum alloy member of the present invention may be widely utilized not only as a member to be used at a temperature within a high temperature range but as other members such as a high strength member for which weight saving is required.
  • molten metal of aluminum alloy comprising each of various alloy compositions listed in Table 1A and Table 1B (referred collectively to as "Table 1") was prepared.
  • the molten alloy was atomized in vacuum atmosphere, and air atomized powder (aluminum alloy powder) was thus obtained.
  • the obtained air atomized powder was classified using a sieve to have a particle diameter of 106 micrometers or less and then used as raw powder.
  • Fig. 5 shows one example of a particle size distribution of the raw powder after the classification (Sample 15 shown in Table 1A).
  • the cavity of a die heated to 150 degrees C was filled with the atomized powder, and compression forming was performed at each of various first pressures (P1) listed in Table 1.
  • P1 various first pressures listed in Table 1.
  • a cylindrical preform having a diameter of 30 mm, 35 mm or 39 mm was obtained (see Fig. 4A ).
  • the relative density of each preform is also listed in Table 1. Each relative density is a value obtained through dividing a bulk density (rho) by a true density (rho0) which is obtained from each aluminum alloy composition, wherein the bulk density (rho) is obtained through dividing a weight of the preform by its volume.
  • each preform was put into a heating furnace and held for 1 hour in nitrogen gas at an atmosphere temperature listed in Table 1. At that time, the nitrogen gas flow rate in the furnace was 10 L/min.
  • Hot forming was performed such that second pressures (P2) listed in Table 1 were applied to respective preforms after the degassing step for a predetermined pressurizing time using Hot Die Coining (HDC).
  • P2 second pressures listed in Table 1
  • each preform was preliminarily reheated to each heating temperature for sparsely compact material listed in Table 1.
  • at least a part of the die (die and punch) to be in contact with the preform was caused to have a die temperature listed in Table 1.
  • molybdenum disulfide (lubricant) was applied to the die surface to be in contact with the preform.
  • each formed body (aluminum alloy member) protruding like a circular truncated cone from a base portion having a diameter of 40 mm (see Fig. 4B ). Except for Sample C3, any of samples was a dense formed body having a formed body density ratio of 0.999 or more obtained in the same manner as that for the preform. Note that the formed body of Sample C3 had a formed body density ratio of 0.989.
  • Fig. 3A is a photograph (SEM image) obtained by observing a fracture surface of the tensile test piece of Sample 15 using a scanning-type electron microscope (SEM), and Fig. 3B is an enlarged photograph of a part thereof.
  • the first pressure and the sparsely compact material density ratio are in a relationship of monotonic increase. It has also been found that the sparsely compact material density ratio can be 0.65 to 0.95 when the first pressure is 100 to 650 MPa. In particular, it has been found that, when the first pressure is about 150 to 400 MPa, a sparsely compact material can be obtained which has a density ratio of about 0.7 to 0.87 and which is thus suitable for the forming method of the present invention. In addition, it has also been confirmed that the increase in the sparsely compact material density ratio is very small even when the first pressure is increased above 650 MPa.
  • the formed body density ratio is around 0.990 when the pressurizing time is 3 seconds; the formed body density ratio is 0.999 when the pressurizing time is 5 seconds; and the formed body density ratio is approximately 1 when the pressurizing time is 10 seconds or more, thus a dense formed body having substantially the true density is obtained.
  • the aluminum alloy powder used in the present examples is a rapidly solidified powder (air atomized powder) obtained such that the alloy elements are forced to form solid solution so that no substantial segregation occurs in the constituent particles. Therefore, the solidus temperature of the aluminum alloy powder is substantially the same as the solidus temperature as referred to in the equilibrium diagram.
  • the "solidus temperature" as used herein may be defined as the solidus temperature in the equilibrium diagram. Note that the solidus temperature is 450 degrees C even in a case of Al-Mg binary system of which the solidus temperature is lowest. Therefore, any forming temperature lower than 450 degrees C is lower than the solidus temperature of all the samples.
  • the formed body (which may substantially be a liquid-phase sintered body) breaks when elastic deformation occurs, and the strength is also considerably low. It appears that this is because locally molten portions are caused at the surfaces and the like of the constituent particles during the forming step, and the molten portions are re-solidified to form an abnormal structure in the formed body (liquid-phase sintered body).
  • the fracture faces appear in the constituent particles rather than at grain boundaries of the constituent particles.
  • the formed body according to the present invention is such that the constituent particles are unified with one another via the metallic bond, and is homogeneous as a whole.
  • Fig. 4C shows an appearance when a cross section obtained by cutting the formed body of Sample 15 is color checked. This also teaches that a dense, homogeneous formed body can be obtained without cracks according to the forming method of the present invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)

Claims (9)

  1. Verfahren zur Bildung eines Aluminiumlegierungspulvers, wobei das Verfahren umfasst:
    einen Pressschritt, bei dem ein erster Druck (P1) auf ein Aluminiumlegierungspulver ausgeübt wird, so dass ein wenig kompaktes Material erhalten wird, wobei das Aluminiumlegierungspulver Mikroteilchen aus einer Aluminiumlegierung mit einem Teilchendurchmesser von 300 Mikrometer oder weniger umfasst, wobei das wenig kompakte Material derart ist, dass die Mikroteilchen durch eine plastische Verformung miteinander verhakt und miteinander in Kontakt sind, während Räume zwischen diesen freibleiben, und
    einen Formgebungsschritt, bei dem ein zweiter Druck (P2) auf das wenig kompakte Material bei einer Formgebungstemperatur ausgeübt wird, so dass ein dichter Formkörper erhalten wird, in dem die Mikroteilchen metallisch aneinander gebunden sind, wobei die Formgebungstemperatur eine Temperatur ist, bei der an Oberflächen der Mikroteilchen keine flüssige Phase auftritt, wobei das Druckverhältnis des zweiten Drucks (P2) zu dem ersten Druck (P1) (P2/P1) 1,2 oder mehr beträgt,
    wobei die Aluminiumlegierung eine Legierungszusammensetzung aufweist, umfassend, wenn deren Gesamtheit als 100 Massen-% (nachstehend einfach als "%" bezeichnet) angesetzt wird,
    Eisen (Fe): 2 bis 7 %,
    Zirkonium (Zr): 0,6 bis 1,5 %,
    Titan (Ti): 0,5 bis 1 % und gegebenenfalls
    Magnesium (Mg): 0,5 bis 2,2 % und
    modifizierende Elemente, umfassend Cr, Mn, Co, Ni, Sc, Y, Ca, V, Hf und Nb,
    wobei es sich bei dem Rest um Aluminium (Al) und unvermeidbare Verunreinigungen handelt.
  2. Verfahren zur Bildung eines Aluminiumlegierungspulvers nach Anspruch 1, bei dem
    der Pressschritt ein Schritt ist, bei dem das Dichteverhältnis des wenig kompakten Materials 0,7 bis 0,95 beträgt, wobei das Dichteverhältnis des wenig kompakten Materials das Verhältnis der Rohdichte des wenig kompakten Materials zu der tatsächlichen Dichte der Aluminiumlegierung ist, und
    der Formgebungsschritt ein Schritt ist, in dem das Dichteverhältnis des Formkörpers 0,97 bis 1 beträgt, wobei das Dichteverhältnis des Formkörpers das Verhältnis der Rohdichte des Formkörpers zu der tatsächlichen Dichte der Aluminiumlegierung ist.
  3. Verfahren zur Bildung eines Aluminiumlegierungspulvers nach Anspruch 1 oder 2, bei dem
    der erste Druck 100 bis 650 MPa beträgt und
    der zweite Druck 500 bis 1000 MPa beträgt.
  4. Verfahren zur Bildung eines Aluminiumlegierungspulvers nach einem der Ansprüche 1 bis 3, bei dem die Formgebungstemperatur niedriger ist als die Solidustemperatur der Aluminiumlegierung.
  5. Verfahren zur Bildung eines Aluminiumlegierungspulvers nach Anspruch 1 oder 4, bei dem die Formgebungstemperatur die Ausscheidungstemperatur oder höher ist, wobei die Ausscheidungstemperatur eine Temperatur ist, bei der eine Verbindungsphase in den Mikroteilchen ausgeschieden wird.
  6. Verfahren zur Bildung eines Aluminiumlegierungspulvers nach einem der Ansprüche 1 bis 5, bei dem der Formgebungsschritt ein Schritt ist, in dem die Zeit des Beaufschlagens mit Druck 5 bis 30 Sekunden beträgt, wobei die Zeit des Beaufschlagens mit Druck eine Zeit ist, während der der zweite Druck auf das wenig kompakte Material bei der Formgebungstemperatur ausgeübt wird.
  7. Verfahren zur Bildung eines Aluminiumlegierungspulvers nach einem der Ansprüche 1 bis 6, das ferner einen Entgasungsschritt umfasst, der Gas entfernt, das nach dem Pressschritt und vor dem Formgebungsschritt in dem wenig kompakten Material vorliegt.
  8. Verfahren zur Bildung eines Aluminiumlegierungspulvers nach einem der Ansprüche 1 bis 7, bei dem die Formgebungstemperatur 350 bis 480 Grad Celsius beträgt.
  9. Aluminiumlegierungselement, das den Formkörper umfasst, der mit dem Verfahren zur Bildung eines Aluminiumlegierungspulvers nach einem der Ansprüche 1 bis 8 erhalten worden ist.
EP13800173.0A 2012-06-08 2013-05-28 Verfahren zum formen eines aluminiumlegierungspulvers und aluminiumlegierungsteil Not-in-force EP2799165B1 (de)

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JP2012131428A JP5772731B2 (ja) 2012-06-08 2012-06-08 アルミニウム合金粉末成形方法およびアルミニウム合金部材
PCT/JP2013/064735 WO2013183488A1 (ja) 2012-06-08 2013-05-28 アルミニウム合金粉末成形方法およびアルミニウム合金部材

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EP2799165A4 EP2799165A4 (de) 2015-11-11
EP2799165B1 true EP2799165B1 (de) 2016-06-29

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JP5772731B2 (ja) 2015-09-02

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