EP2056984A1 - Procédé de moulage par injection de métal - Google Patents

Procédé de moulage par injection de métal

Info

Publication number
EP2056984A1
EP2056984A1 EP07784748A EP07784748A EP2056984A1 EP 2056984 A1 EP2056984 A1 EP 2056984A1 EP 07784748 A EP07784748 A EP 07784748A EP 07784748 A EP07784748 A EP 07784748A EP 2056984 A1 EP2056984 A1 EP 2056984A1
Authority
EP
European Patent Office
Prior art keywords
aluminium
binder
sintering
oxygen
getter
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP07784748A
Other languages
German (de)
English (en)
Inventor
Zhenyun Liu
Timothy Barry Sercombe
Graham Barry Schaffer
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
University of Queensland UQ
Original Assignee
University of Queensland UQ
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from AU2006904265A external-priority patent/AU2006904265A0/en
Application filed by University of Queensland UQ filed Critical University of Queensland UQ
Publication of EP2056984A1 publication Critical patent/EP2056984A1/fr
Withdrawn legal-status Critical Current

Links

Classifications

    • 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
    • B22F3/22—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces for producing castings from a slip
    • B22F3/225—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces for producing castings from a slip by injection molding
    • 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
    • B22F3/1003—Use of special medium during sintering, e.g. sintering aid
    • B22F3/1007—Atmosphere
    • 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
    • B22F3/1021—Removal of binder or filler
    • B22F3/1025—Removal of binder or filler not by heating only
    • 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
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy

Definitions

  • the present invention relates to a metal injection moulding method.
  • Metal injection moulding involves the mixing of powder metal with a binder to form a feedstock. This mixture is then injection moulded using injection moulding equipment that is similar to that used in the plastics industry. This forms a "green body". The green body has sufficient rigidity and strength to enable handling. The green body is then further treated to remove the binder and to sinter the metal powder particles to form the final article.
  • the binder typically comprises one or more thermoplastic compounds, plasticisers and other organic material. Ideally, the binder is molten or liquid at the injection moulding temperature but solidifies in the mould when the green body is cooled.
  • the feedstock may be converted into solid pellets, for example by granulation. These pellets may be stored and fed into the injection moulding machine at a later time.
  • Typical injection moulding equipment includes a heated screw or extruder having a nozzle through which the mixture is extruded into the die cavity.
  • the extruder is heated to ensure that the binder is in liquid form and the nozzle temperature is typically carefully controlled to ensure constant conditions.
  • the temperature of the die is also controlled so that the temperature is low enough to ensure that the green body is rigid when it is removed from the die.
  • the green body will be larger than the final article.
  • Further processing of the green body involves removing the binder and sintering.
  • the binder may be completely removed before sintering.
  • the binder may be partly removed before the sintering step, with complete removal of the binder being achieved during the sintering step. Removal of the binder may take place by using a solvent to dissolve the binder or by heating the green body to cause the binder to melt, decompose and/or evaporate. A combination of solvent removal and thermal removal may also be used.
  • the sintering step involves heating the body to cause the separate metal particles to metallurgically bond together.
  • Sintering in the production of metal injection moulded parts is generally similar to sintering used in the production of traditional powder metal parts.
  • Non-oxidising atmospheres are typically used during the sintering step in order to avoid oxidation of the metal.
  • the very porous body remaining after removal of the binder densities and shrinks.
  • the sintering temperature and temperature distribution will typically be closely controlled in order to retain the shape of the article during sintering and to prevent distortion of the article. In this fashion, net shape articles can be recovered from the sintering step.
  • Metal injection moulding is suitable for producing articles from almost any metal that can be produced in a suitable powder form.
  • aluminium is difficult to use in metal injection moulding because the adherent aluminium oxide film that is always present on the surface of particles of aluminium or aluminium alloy inhibits sintering.
  • United States Patent No. 6,761,852 assigned to Advanced Materials Technologies Pte Ltd, describes a metal injection moulding process for forming objects from aluminium and its alloys.
  • a powder of aluminium or an aluminium alloy is mixed with a powder containing a material that is said to form a eutectic with aluminium oxide, such as silicon carbide or a metallic fluoride.
  • This mixed powder is then mixed with a binder, injection moulded, subject to removal of the binder, and sintered.
  • the silicon carbide or metal fluoride is said to form a eutectic mixture with aluminium oxide which supposedly dissolves the aluminium oxide, thereby allowing intimate contact between aluminium surfaces during the sintering step.
  • the present invention provides a method for forming an article by metal injection moulding of aluminium or an aluminium alloy, the method comprising the steps of:
  • the oxygen-getter may comprise any metal that has a higher affinity for oxygen than aluminium.
  • suitable metals for use as the oxygen-getter include the alkali metals, the alkaline earth metals and the rare earth metals. Where one or more rare earth metals are used as the oxygen-getter, it is preferred that rare earth metals from the lanthanide series are used.
  • Magnesium is the preferred metal for use as the oxygen-getter because it is has a high vapour pressure, it is readily available and it is relatively inexpensive.
  • blocks of the oxygen-getter may be positioned around the article that is being sintered during the sintering step.
  • powder of the oxygen-getter may be placed around or on the article that is being sintered during the sintering step.
  • the oxygen-getter may be mixed in with the aluminium or aluminium powder alloy, or mixed in with the mixture that is fed to the injection moulding apparatus.
  • the oxygen getter is present as a component of an alloy added to the mixture, such as being present in an alloy powder added to the mixture.
  • powder of an alloy containing aluminium and magnesium may be added to the mixture or incorporated into the mixture.
  • some alloys that can be incorporated into the mixture include Al-7.9wt%Mg and Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si.
  • the oxygen-getter removes any oxygen that may be present in the atmosphere surrounding the part during the sintering step.
  • the oxygen-getter may also act to reduce the aluminium oxide that surrounds the aluminium or aluminium alloy particles. This assists in disrupting the aluminium oxide layer around the particles, exposing fresh metal, thereby allowing sintering of the aluminium or aluminium alloy particles to take place.
  • magnesium is a suitable oxygen-getter.
  • magnesium also has a high vapour pressure. Consequently, during the sintering step (which takes place at elevated temperature), magnesium vapour may surround the article that is being sintered.
  • a sintering aid is added to the mixture prior to injection moulding of the mixture.
  • the sintering aid is a low melting point metal.
  • the sintering aid may be a metal that has a melting point that is lower than the melting point of aluminium.
  • the sintering aid comprises a low melting point metal that is insoluble in solid aluminium.
  • suitable sintering aids include tin, lead, indium, bismuth and antimony. It has been found that tin is especially suitable in assisting in sintering of aluminium and aluminium alloys. Therefore, tin is a preferred sintering aid.
  • Tin is a preferred sintering aid for use in the present invention because it has been found that tin suppresses the formation of aluminium nitride during sintering (thereby avoiding formation of excessive aluminium nitride, which might have a detrimental effect on the properties of the final article) and also changes the surface tension of molten aluminium, thereby promoting good distribution of liquid aluminium phase during sintering.
  • the sintering aid may be added in an amount of up to 10% by weight, based upon the total weight of the metal powder and the sintering aid.
  • the sintering aid is present in an amount of from 0.1% to 10% by weight, more preferably 0.5% to 3% by weight, even more preferably about 2% by weight.
  • tin is used as the sintering aid, it may be added in an amount of from 0.1% to 10%, more suitably from 0.5% to 4%, even more suitably from 0.5% to 2.0% by weight of the mixture.
  • the sintering step is conducted in a nitrogen atmosphere.
  • conducting the sintering step in a nitrogen atmosphere may promote the formation of aluminium nitride.
  • forming aluminium nitride in the sintering step may assist in disrupting or breaking down the aluminium oxide film that normally surrounds the particles of aluminium or aluminium alloy.
  • the use of tin as a sintering aid may also assist in controlling the formation of AlN as formation of excessive amounts of AlN during sintering may cause detriment to the properties of the final article.
  • the present inventors have found that conducting sintering of aluminium powder in a nitrogen atmosphere can result in the rapid conversion of the aluminium to aluminium nitride. Due to the rapid rate at which the aluminium can be converted to aluminium nitride in these circumstances, there is a risk that the entire article may be converted to aluminium nitride. Using tin as a sintering aid acts to limit the formation of excess AlN in such circumstances.
  • the present inventors have postulated that the nitrogen atmosphere disrupts the aluminium oxide film on the surface of the aluminium or aluminium alloy particles by forming aluminium nitride. It is further postulated that this disruption of the aluminium oxide film enables sintering of the aluminium or aluminium alloy particles to occur.
  • the atmosphere in which the sintering step is conducted may have a low water content, for example, it may have a water vapour partial pressure of less than 0.00 IkPa.
  • the atmosphere used on the sintering step may have a dew point of less than -60°C, more preferably, less than -70°C.
  • Magnesium when used as an oxygen getter, reacts with oxygen and water, thereby further lowering the water content of the atmosphere. It is believed that water vapour is extremely detrimental to the sintering of aluminium.
  • the atmosphere is an atmosphere containing nitrogen.
  • the atmosphere may be predominantly nitrogen.
  • the atmosphere may be 100% nitrogen.
  • the atmosphere may also include an inert gas.
  • the inert gas may comprise a minor part of the atmosphere.
  • the atmosphere may be essentially free of oxygen and hydrogen.
  • the gas that is supplied as the atmosphere during sintering suitably contains no oxygen or hydrogen.
  • the binder used in the present invention may be any binder or binder composition known to be suitable for use as a binder in metal injection moulding.
  • the binder is typically an organic component or a mixture of two or more organic components.
  • the binder desirably includes thermoplastic components that enable the binder to melt upon application of heat.
  • the binder should also impart sufficient strength to the green body following injection moulding to enable the green body to be handled.
  • the binder is able to be removed from the green body in a manner that retains integrity of the body during the binder removal process. It is preferable that the binder leaves no residue following removal.
  • the binder may be made from two or more materials. The two or more materials that comprise the binder may be selected such that they may be sequentially removed from the green body. In this fashion, a controlled removal of the binder is more easily achieved, thereby facilitating retention of shape integrity of the body during binder removal. In this regard, it will be appreciated that if the binder is removed too rapidly, the risk of the body losing its shape integrity is increased.
  • the binder may be removed by one or more of the known techniques used in metal injection moulding for removing the binder.
  • the binder may be removed by dissolution in a solvent, by thermal treatment to cause the binder to melt, evaporate or decompose, by catalytic removal of the binder or by wicking.
  • Two or more binder removal techniques may be used in the binder removal stage.
  • a first step in the binder removal may involve solvent extraction, followed by thermal removal of the remainder of the binder.
  • binder materials include organic polymers such as stearic acid, waxes, paraffin and polyethylene.
  • the present inventors have used a binder comprising stearic acid, palm oil wax and high density polyethylene in experimental work relating to the present invention.
  • the sintering step used in the present invention involves heating the green body to a temperature at which the aluminium or aluminium alloy sinters to form a dense body.
  • the sintering step suitably involves heating to a temperature within the range of about 550°C to about 650°C, more suitably 59O 0 C to 64O 0 C, most suitably between 610 0 C to 630°C.
  • the sintering time may vary. Typically, a shorter sintering time may be used for a higher sintering temperature. Essentially, the sintering time should be long enough to ensure that maximum densification of the article has occurred. Sintering at temperatures of from 620 0 C to 63O 0 C for up to two hours has been found to provide satisfactory results.
  • heating rates and thermal profile used in the sintering step are normally closely controlled in metal injection moulding methods to obtain optimum properties in the final article.
  • the person skilled in the art will readily understand how to determine suitable heating rates and temperature profiles for use in the sintering step.
  • the method of the present invention is suitable for use with aluminium metal and aluminium alloys.
  • Any aluminium alloy can be used in the present invention, including aluminium alloys from the 1000 series, 2000 series, 3000 series, 4000 series, 5000 series, 6000 series, 7000 series and 8000 series.
  • Ceramic particles can be mixed with the aluminium or aluminium alloy powders to create an aluminium metal matrix composite.
  • the ceramic particles are used to improve or control the properties of the sintered article. Such properties can include, but are not limited to, wear resistance, stiffness or coefficient of thermal expansion.
  • a non- exhaustive list of typical ceramic materials include SiC, Al 2 O 3 , AlN, SiO 2 , BN and TiB 2 .
  • the method of the present invention may be carried out in known metal injection moulding apparatus.
  • Figure 1 shows a photomicrograph of the fracture surface of a test bar made in accordance with an embodiment of the present invention following debinding
  • Figure 2 shows photographs of a green body and a sintered body for test bars made in accordance with an embodiment of the present invention
  • Figure 3 is a graph of density and hardness of test pieces made in accordance with embodiments of the present invention.
  • Figure 4 shows graphs of tensile curves of test bars after sintering at various conditions
  • Figure 5 shows microstructures of sintered products made in accordance with an embodiment of the present invention
  • Figure 6 shows a graph of the effect of elemental Mg additions on sintered density
  • Figure 7 shows the liquid content as a function of temperature for the alloys listed in Figure 7;
  • Figure 8 shows a graph of the sintered density of AA6061+X%Sn loose powders as a function of temperature
  • Figure 9 shows a graph of sintered density as a function of temperature for the feedstock mixtures listed in that Figure.
  • the metal injection moulding feedstock consisted of 6061 powder with 2wt% Sn and a binder system of 3wt% stearic acid, 52wt% palm oil wax and 45wt% high density polyethylene. The raw materials were mixed at 165°C for 180 minutes. After granulating, the feedstock was injection moulded into standard tensile bars using an Arburg moulding machine. Solvent debinding was conducted in hexane at 40°C for 24 hours.
  • the removal of the remaining binder and sintering were combined and conducted in a sealed tube furnace.
  • the preferred atmosphere is high purity nitrogen gas flowing at 1 litre/min.
  • the thermal profile used in the experimental work is shown in Table 1. Magnesium bars were placed around the article during sintering.
  • Figure 1 shows a fracture surface of a debound part. The powder morphology has not changed from the original.
  • Figure 2 shows the injection moulded (green) body and the sintered part.
  • the sintered part is free of defects such as blisters, cracks and warpage. It also has a good surface finish.
  • Figure 3 shows the density and hardness of the test bars under various sintering conditions.
  • the sintered density was 90.0+0.6% and the hardness was 39.1+12.3.
  • the big variation of hardness is possibly due to the high porosity level.
  • the sintering time was increased to 2 hours, the density and hardness increased to 94.9+0.3% and 66.9+2.9, respectively.
  • further increasing the sintering temperature to 630 0 C did not significantly increase the density and hardness.
  • the density in this condition was 95.3+0.3% and the hardness was 69.0 ⁇ 0.9.
  • Typical stress/strain curves of parts sintered at various conditions are plotted in Figure 4.
  • the part sintered at 620°C for 2 hours has the best mechanical properties and recorded a 0.2% yield strength of 58 MPa, a tensile strength of 156 MPa and elongation to failure of 8.9%.
  • the tensile properties of the parts sintered at 630°C were slightly lower than this, despite the higher density. This was possibly due to microstructural coarsening at the higher sintering temperature.
  • Figure 5 shows the micro structure of a sample after sintering at 620°C for 2 hours.
  • the optical micrograph shows that the grain size remains at about the original particle size and is less than 20 ⁇ m.
  • the backscattered electron image shows the distribution and size of the Sn rich phase (white contrast in electron image, black contrast in optical image). No obvious pores were visible.
  • Pre-alloyed powders of composition Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si and Al- 7.9 wt%Mg were obtained from the Aluminium Powder Company.
  • the Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si powders have an average particle size of about 25 ⁇ m whilst the Al- 7.9 wt%Mg powders have an average particle size of about 40 ⁇ m. Both have a regular particle shape.
  • the Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si has a solidus temperature around 540°C and it is fully liquefied at 600°C.
  • the Al-7.9 wt%Mg has a solidus temperature around 54O 0 C and it is fully liquefied at 62O 0 C.
  • Figure 7 illustrates the liquid content as a function of temperature for these alloys, as well as alloy AA6061 and for a mixture of AA6061 + 7.5wt% Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si. It has been found that sintering a mixture of AA6061 + 7.5% Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si + 2wt% Sn feedstock at 610°C for two hours in nitrogen produces distortion free parts which have a density of -97% of theoretical.
  • Sn has been used as an effective sintering additive for the pressed or un- compacted aluminium alloys and compacts prepared by rapid prototyping processes.
  • the present inventors have demonstrated that Sn plays an important role in the sintering of tapped loose powders and powder injection moulded aluminium compacts.
  • Sn will remain at the grain boundaries after sintering since tin is almost insoluble in solid aluminium. Excess amounts of tin will deteriorate the mechanical properties, especially the ductility, which is extremely desirable for aluminium alloys prepared from powders.
  • the debound part (brown part) of powder injection moulded aluminium compact only has a relative density about ⁇ 85%. After the polymer binders are removed, there are open channels connecting to the part surface in the porous debound part. Tapped loose powders only have a relative density about 40 ⁇ 60%, connected pores may form open channels to the surface. Significant amount of liquid is needed to seal these channels.
  • 4% Sn helps the sintering of loose compacted pure aluminium powders; addition of 2% Sn enhanced the sintering of powder injection moulded AA6061 compact.
  • the addition of the heavily pre-alloyed powders will also help increase alloy content in the sintered part and improve its strength.
  • the decrease of Sn content may help to improve ductility. By such means, the mechanical properties of the alloy system could be further improved.
  • Elemental Sn ( ⁇ 43 ⁇ m) is used as a sintering aid to enhance the liquid phase sintering of fine AA6061 powders ( ⁇ 20 ⁇ m) mixed with pre-alloyed Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si powder ( ⁇ 30 ⁇ m).
  • the powders were mixed in a Turbula mixer for 30 minutes according to the formulation of AA6061+Xwt%Sn+Ywt%Al-2 wt%Cu-9.3 wt%Mg-5.4 wt%Si.
  • the mixed powders were poured into alumina crucibles, tapped and enclosed by aluminium foils.
  • the sintered density was ⁇ 95% or higher for the alloys with 1.0 or 2.0wt% Sn in the sintering temperature window of 600 ⁇ 630°C.
  • AA6061 loose powders without Sn only achieved 83%, 88% and 93% at 61O 0 C, 620 0 C and 63O 0 C, respectively.
  • the liquid volume is one of the most critical factors for the densification and part shape retention.
  • the liquid volume in the Al-Sn alloy system is controlled by temperature, aluminium alloy composition and the Sn content.
  • Figure 7 shows the effect of temperature on the liquid volume fraction for the tested alloys. This data was calculated using ThermoCalc. No Sn addition is considered.
  • Al-2wt%Cu-9.3wt%Mg-5.4wt%Si alloys the calculations were based on the final total alloy content.
  • the pre-alloyed Al-2wt%Cu-9.3wt%Mg-5.4wt%Si powder has a solidus of 582 0 C and it is fully liquefied at 604 0 C.
  • this alloy will be very difficult in process control with such a narrow melting window if it is sintered alone.
  • this early formed liquid with high Mg content may scavenge oxygen in the sintering furnace and help to seal the open channels in the loose powders before serious oxidation occurs, which usually starts at about 580 ⁇ 600°C.
  • Figure 9 shows the sintered density of AA6061+0.5wt%Sn loose powders with addition of 0%, 2.5% and 7.5% pre-alloyed Al-2wt%Cu-9.3wt%Mg-5.4wt%Si powders after sintering at various temperatures for 2 hours in nitrogen.
  • the sintered density of AA6061+0.5wt%Sn increases steadily as function of temperature till 630°C as liquid volume increase.
  • the liquid from the melting of Al-2wt%Cu-9.3wt%Mg-5.4wt%Si powders sharply increased the density at sintering temperature of 600 0 C for 2.5wt% addition and 59O 0 C for 7.5wt% addition.

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

Abstract

L'invention concerne un procédé pour former un article par moulage par injection de métal d'aluminium ou d'un alliage d'aluminium. Le procédé comprend les étapes de formation d'un mélange contenant une poudre d'aluminium ou une poudre d'un alliage d'aluminium, ou les deux, et éventuellement des particules de céramique, un liant et un précurseur de frittage comprenant un métal à bas point de fusion. Le mélange est moulé par injection et le liant est enlevé pour former un corps vert. Le corps vert est fritté. Le frittage est réalisé dans une atmosphère qui contient de l'azote et en présence d'un capteur d'oxygène.
EP07784748A 2006-08-07 2007-08-07 Procédé de moulage par injection de métal Withdrawn EP2056984A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AU2006904265A AU2006904265A0 (en) 2006-08-07 Metal Injection Moulding of Aluminium Alloys and Composites
PCT/AU2007/001108 WO2008017111A1 (fr) 2006-08-07 2007-08-07 Procédé de moulage par injection de métal

Publications (1)

Publication Number Publication Date
EP2056984A1 true EP2056984A1 (fr) 2009-05-13

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP07784748A Withdrawn EP2056984A1 (fr) 2006-08-07 2007-08-07 Procédé de moulage par injection de métal

Country Status (7)

Country Link
US (1) US20100183471A1 (fr)
EP (1) EP2056984A1 (fr)
JP (1) JP2010500469A (fr)
CN (1) CN101594954A (fr)
AU (1) AU2007283448A1 (fr)
CA (1) CA2660484A1 (fr)
WO (1) WO2008017111A1 (fr)

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WO2009029993A1 (fr) * 2007-09-07 2009-03-12 The University Of Queensland Procédé de moulage par injection de métal
WO2009029992A1 (fr) * 2007-09-07 2009-03-12 The University Of Queensland Procédé de moulage par injection de métal
JP5182648B2 (ja) * 2008-03-18 2013-04-17 日立金属株式会社 多孔質アルミニウム焼結体の製造方法
JP5639329B2 (ja) * 2008-03-28 2014-12-10 日信工業株式会社 複合金属材料の製造方法及び複合金属材料
JP5492550B2 (ja) * 2009-12-28 2014-05-14 株式会社Ｉｈｉ 脱脂方法
AT509613B1 (de) * 2010-04-01 2017-05-15 Technische Universität Wien Verfahren zur herstellung von formköpern aus aluminiumlegierungen
US9533351B2 (en) * 2010-10-04 2017-01-03 Gkn Sinter Metals, Llc Aluminum powder metal alloying method
MY174986A (en) * 2011-04-12 2020-05-31 Institute For Medical Res Maxillofacial implant by an injection molding of metal powders (mim) using a binder-system of palm oil derivatives
DK2709967T3 (da) * 2011-05-18 2019-07-29 Basf Se Fremgangsmåde til fremstilling af elementer i pulversprøjtestøbningsfremgangsmåde
KR20130025717A (ko) * 2011-09-02 2013-03-12 삼성디스플레이 주식회사 유기 발광 표시 장치 및 유기 발광 표시 장치 제조 방법
CN103008662B (zh) * 2011-09-23 2015-06-03 复盛应用科技股份有限公司 复合金属的一体成型方法
FR2990894B1 (fr) * 2012-05-25 2014-06-13 Seb Sa Couteau de tondeuse autolubrifiant et son procede de fabrication
KR20140048428A (ko) * 2012-10-15 2014-04-24 현대자동차주식회사 금속분말 사출 성형을 이용한 컨트롤 핑거의 제조방법
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JP6488875B2 (ja) * 2014-05-16 2019-03-27 三菱マテリアル株式会社 多孔質アルミニウム焼結体及び多孔質アルミニウム焼結体の製造方法
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CN101594954A (zh) 2009-12-02
AU2007283448A1 (en) 2008-02-14

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