EP2200770A1 - Procédé de production d'une pièce en métal à base de poudre durcissable par frittage - Google Patents

Procédé de production d'une pièce en métal à base de poudre durcissable par frittage

Info

Publication number
EP2200770A1
EP2200770A1 EP08784503A EP08784503A EP2200770A1 EP 2200770 A1 EP2200770 A1 EP 2200770A1 EP 08784503 A EP08784503 A EP 08784503A EP 08784503 A EP08784503 A EP 08784503A EP 2200770 A1 EP2200770 A1 EP 2200770A1
Authority
EP
European Patent Office
Prior art keywords
weight
powder
sintering
range
lower limit
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Withdrawn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
EP08784503A
Other languages
German (de)
English (en)
Inventor
Gerold Stetina
Jürgen VOGLHUBER
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.)
Miba Sinter Austria GmbH
Original Assignee
Miba Sinter Austria GmbH
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
Application filed by Miba Sinter Austria GmbH filed Critical Miba Sinter Austria GmbH
Publication of EP2200770A1 publication Critical patent/EP2200770A1/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Withdrawn legal-status Critical Current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
    • B22F3/10—Sintering only
    • B22F3/1017—Multiple heating or additional steps
    • B22F3/1021—Removal of binder or filler
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0207—Using a mixture of prealloyed powders or a master alloy
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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 invention relates to a method of producing a sinter-hardenable powder metal part from a sinter powder containing chromium, comprising the steps of preparing the sinter powder, compacting the sinter powder to form a green compact, pre-sintering the green compact to form a brown compact under a reducing atmosphere followed by slow cooling, calibrating the brown compact and high-temperature sintering of the calibrated brown compact followed by rapid cooling, and further relates to a sinter-hardened powder metal part with an iron base powder containing chromium.
  • a method of producing sinter-hardened powder metal parts for the automotive industry is known from patent specification DE 101 96 487 Tl, whereby a metallurgical powder of iron containing between 1.0 % by weight and 3.0 % by weight of copper and containing between 0.3 % by weight and 0.8 % by weight of carbon is compressed to form a compressed body at a pressure in the range of between 20 tsi and 70 tsi, the compressed body is then heated to a temperature of 2000° F to 2400° F and maintained at this temperature for at least 15 minutes in order to produce a sintered compressed body.
  • This compressed body is then cooled at a cooling rate of no more than 60° F/min, as a result of which a compressed body with a hardness of no more than RC25 is obtained.
  • the density in at least the surface region of this com- pressed body is then increased to at least 7.6 g/cm 3 , after which this sintered compressed body is sintered in a final process at a temperature of from 2050° F to 2400° F for at least 20 minutes. After the final sintering process, it is cooled rapidly at a cooling rate of from 120° F/min to 400° F/min, as a result of which the hardness is increased to more than RC25.
  • the metallurgical powder may also contain nickel, molybdenum, chromium, manganese and vanadium, in which case the molybdenum content may be in the range of between 0 % by weight and 2.0 % by weight, that of the nickel is in the range of between 0 % by weight and 3.0 % by weight, that of the manganese is between 0 % by weight and 0.7 % by weight and that of the chromium is between 0 % by weight and 4.0 % by weight.
  • chromium is mentioned as a possible alloying component in this DE-Tl, it has been found that iron-based powders containing chromium, in particular highly alloyed chromium steels, can not be processed with the method defined in the DE-TI or can be so only with great difficulty, and more especially the high densities of the finished sintered component can not be achieved.
  • the DE-Tl also states that a less desirable sinter powder amongst others is one of the type QMP4701, which contains 0.9 % by weight of nickel, 1 % by weight of molybdenum, 0.45 % by weight of manganese and 0.5 % by weight of chromium, with iron making up the rest.
  • the objective of this invention is to propose a sinter hardening method for processing iron- based powders containing chromium as well as corresponding powder metal parts.
  • This objective is achieved by the invention respectively by the method outlined above where- by the pre-sintering process is conducted at a temperature selected from a range with a lower limit of 700°C and an upper limit of 1050°C and by a sinter-hardened powder metal part based on an iron powder containing chromium, the body of the part having a density of at least 7.2 g/cm 3 .
  • the method proposed by the invention therefore enables powder metal parts containing chromium to be produced from an iron-based powder, which have a density almost corresponding to the full density but at least 7.2 g/cm 3 . This method also results in a very homogeneous structure of the powder metal parts.
  • the temperature during pre-sintering may also be selected from a range with a lower limit of 750 °C and an upper limit of 1000°C, in particular from a range with a lower limit of 775 °C and an upper limit of 950 0 C.
  • the body of the part has a density with a lower limit of 7.2 g/cm 3 and an upper limit of 7.5 g/cm 3 .
  • the reducing atmosphere during pre-sintering and optionally during high-temperature sintering may be a nitrogen-hydrogen mixture, which contains a proportion of hydrogen selected from a range with a lower limit of 0 % by volume, in particular 5 % by volume, and an upper limit of 30 % by volume.
  • a proportion of hydrogen selected from a range with a lower limit of 0 % by volume, in particular 5 % by volume, and an upper limit of 30 % by volume.
  • the proportion of hydrogen in the atmosphere may also be selected from a range with a lower limit of 7 % by volume and an upper limit of 25 % by volume, in particular from a range with a lower limit of 10 % by volume and an upper limit of 15 % by volume.
  • a carburizing gas is added to the reducing atmosphere during pre- sintering and optionally high-temperature sintering or a carburizing gas is used as a reducing atmosphere.
  • this enables the carbon content in at least the surface regions of the finished powder metal part to be increased, which is conducive to the formation of martensite during the rapid cooling proc- ess which follows the high-temperature sintering.
  • pre-sintering can be conducted at a lower temperature than described in the prior art because higher carbon contents can be achieved without the risk of the hardness of the brown compact being too high for the subsequent calibration.
  • the brown compact may also be cooled at a rate selected from a range with a lower limit of 0.1 K/s and an upper limit of 2 K/s in order to avoid premature hardening of the brown compact as far as possible or reduce the degree of hardening.
  • the cooling rate may be selected from a temperature range with a lower limit of 0.7 K/s, in particular 0.5 K/s. By increasing the lower limit, premature hardening can be even more effectively avoided.
  • the brown compact is preferably calibrated to a density of at least 7. 2 g/cm 3 prior to high-temperature sintering.
  • the calibration is effected to a density selected from a range with a lower limit of 7.2 g/cm 3 and an upper limit of 7.5 g/cm 3 , in other words a density which corresponds to almost the full density of the material.
  • the sinter powder used is preferably an iron-based powder.
  • This iron-based powder may contain chromium in a proportion selected from a range with a lower limit of 1 % by weight and an upper limit of 5 % by weight. This proportion may be in pre-alloyed form or may be added by some other means used in sintering technology (such as in the form of ferro-alloys for example).
  • highly alloyed chromium steels may be produced using the method proposed by the invention, which - in a known manner — have an excellent resistance to corrosion and very high hardness levels.
  • the hardness may be between 250 HV5 and 600 HV5.
  • the proportion of chromium may also be selected from a range with a lower limit of 1.2 % by weight and an upper limit of 4 % by weight, in particular from a range with a lower limit of 1.5 % by weight and an upper limit of 3 % by weight.
  • the properties of such iron-based powder metal components can be improved accordingly, as is already the case in the prior art with steels.
  • non-iron alloying elements such as copper, nickel, manganese, silicon, mo- lybdenum and vanadium
  • the properties of such iron-based powder metal components can be improved accordingly, as is already the case in the prior art with steels.
  • molybdenum to the alloy, the initial brittleness of such chromium steels can be prevented. This improves hardenability and toughness.
  • the creep resistance at higher temperatures can also be increased.
  • Nickel enables the cold forming capacity to be improved.
  • Manganese im- proves tensile strength and yield strength. During tempering, silicon prevents the precipitation of cementite from the martensite.
  • the proportion of non-iron alloying elements may also be selected from a range with a lower limit of 0.2 % by weight and an upper limit of 8 % by weight, in particular from a range with a lower limit of 1 % by weight and an upper limit of 6 % by weight.
  • copper may be used in a proportion selected from a range with a lower limit of 0 % by weight and an upper limit of 6 % by weight, in particular from a range with a lower limit of 0.1 % by weight and an upper limit of 4 % by weight, preferably from a range with a lower limit of 0.2 % by weight and an upper limit of 2 % by weight.
  • the proportion of nickel may be selected from a range with a lower limit of 0 % by weight and an upper limit of 8 % by weight, in particular from a range with a lower limit of 0.1 % by weight and an upper limit of 4 % by weight, preferably from a range with a lower limit of 0.2% by weight and an upper limit of 2 % by weight.
  • the proportion of manganese may be selected from a range with a lower limit of 0 % by weight and an upper limit of 10 % by weight, in particular from a range with a lower limit of 0.1 % by weight and an upper limit of 5 % by weight, preferably from a range with a lower limit of 0.2 % by weight and an upper limit of 2 % by weight.
  • the proportion of molybdenum may be selected from a range with a lower limit of 0 % by weight and an upper limit of 3 % by weight, in particular from a range with a lower limit of 0.1 % by weight and an upper limit of 1.5 % by weight, preferably from a range with a lower limit of 0.2 % by weight und an upper limit of 0.85 % by weight.
  • the proportion of silicon may be selected from a range with a lower limit of 0 % by weight and an upper limit of 5 % by weight, in particular from a range with a lower limit of 0.1 % by weight and an upper limit of 2 % by weight, preferably from a range with a lower limit of 0.2% by weight and an upper limit of 0.5 % by weight.
  • the proportion of vanadium may be selected from a range with a lower limit of 0 % by weight and an upper limit of 8 % by weight, in particular from a range with a lower limit of 0.1 % by weight and an upper limit of 2 % by weight, preferably from a range with a lower limit of 0.2 % by weight and an upper limit of 0.5 % by weight.
  • the proportion of graphite may also be selected from a range with a lower limit of 0.2 % by weight and an upper limit of 1.9 % by weight, in particular from a range with a lower limit of 0.4 % by weight and an upper limit of 0.8 % by weight.
  • a compacting agent is added to the iron-based powder in a quantity of up to 3 % by weight and/or an organic binding agent in particular in a quantity of up to 1 % by weight.
  • This also makes it possible to create a porosity due to these agents burning out during pre-sintering, which makes subsequent compaction during the calibration easier, which in turn brings the advan- tage of being able to use a lower temperature during pre-sintering and avoids or reduces diffusion processes.
  • it also simplifies the operation of compressing sinter powders which are difficult to compress, such as sinter powders containing chromium. Above a total of 4 % by weight of agents, the porosity may be too high, which can lead to lower final densities of the finished sintered component under certain circumstances.
  • the proportion of compacting agent may also be up to 2.5 % by weight, in particular 2 % by weight, and the proportion of binding agent may be up to 0.75 % by weight, in particular 0.5% by weight.
  • the rapid cooling after high-temperature sintering may be run at a cooling rate selected from a range with a lower limit of 2 K/sec and an upper limit of 16 K/sec. This can be conducive to creating the martensitic hardness pattern, especially if the high-temperature sintering process is conducted in a carburizing medium, and internal stress curves can be achieved which are favourable in terms of mechanical properties, in particular fatigue properties.
  • the cooling rate may also be selected from a range with a lower limit of 2.5 K/sec and an upper limit of 15 K/sec, in particular from a range with a lower limit of 3 K/sec and an upper limit of 10 K/sec.
  • tempering temperature is prefera- bly not in excess of 250° C so as to avoid reducing the high martensite hardness.
  • the tempering temperature is a max. of 200 ° C, preferably max. 180° C.
  • the upward rate during tempering is optimally in the range of between 2 K/min and 30 K/min.
  • the proportion of carbon decreases from an ex- ternal surface in the direction towards a core of the body of the formed part following a gradient, as a result of which this powder metal part will have a high surface hardness whilst simultaneously exhibiting a good toughness at the core.
  • the proportion of carbon may decrease from 0.5 % by weight at the surface to 0.35 % by weight in a coating thickness of 0.1 mm, for example, following a linear or an exponential curve.
  • the formed body of the powder metal part may be a sliding sleeve or a coupling element.
  • the invention relates to a method of producing sintered components for automotive applications with densities of >7.2 g/cm 3 from powders which are not so easy or difficult to compress.
  • the components are subjected to powder pressing processes in order to obtain densities of >7.1 g/cm 3 , released and pre-sintered to a density of >7.35, calibrated in the pre-sintered state and then hardened by sintering.
  • the powders which are medium to difficult to compact comprise hybrid, pre-alloyed or alloyed iron powders which serve as base powders and cause an alloy to form due to diffusion during sintering as a result of adding other alloy powders (in commercially available states or degrees of purity) such as Cu, Ni, Mn, Cr, Si, Mo, V, etc., as well as graphite and pressing agents.
  • alloy systems are formulated so that a cooling process run after sintering at cooling rates of approximately 2 to 16 K/s will cause the component to harden.
  • the advantage of hybrid alloys is that these hardening alloy elements are already distributed accordingly in the micro-structure.
  • Medium to difficult to press iron powder mixtures are prepared containing chromium in a proportion of up to 4 % by weight and with a total of up to 10 % by weight of metallic non-iron alloy elements, up to 5 % by weight of graphite, up to 3 % by weight of pressing agents and up to 1 % by weight of organic binding agents. These mixtures are either pre-mixed in a so- called master mixture in a highly concentrated form, optionally also using temperature and solvents, and are then admixed with iron powder in the relevant quantities or are added directly to the iron powder by adding the individual elements.
  • the binding agents used may be resins, silanes, oils, polymers or adhesives. Pressing agents include stearates, silanes, amides and polymers, amongst others.
  • Pre-alloying elements may be Cr, Mo, V, Si, Mn.
  • Hybrid alloy powders may be Fe powder pre-alloyed with Cr-Mo containing diffusion- alloyed Ni and/or Cu, Fe powder pre-alloyed with Mo containing Ferro-Cr and Ferro-Mn, even if these are diffusion-alloyed.
  • the iron powder mixtures above, pre-treated by the method described above, are compacted by coaxial pressing methods and shaped. In this respect, care must be taken to ensure that allowance is already made for the changes in shape and structure that will occur during the subsequent process steps when manufacturing the pressing tools. It is helpful to use appropriate lubricants and binding agents when compacting to densities of >7.1g/cm 3 with powders that are medium to difficult to press. Depending on the bulk density and theoretical density of the powder mixtures, pressing pressures of 600 to 1200 MPa are used for this purpose.
  • the mouldings (also referred to as green compacts) obtained in this manner are the starting point for the subsequent process steps.
  • the mouldings are pre-sintered by a thermal treatment under the effect of gases creating a reducing atmosphere.
  • reducing atmospheres can be created using nitrogen-hydrogen mixtures with a proportion of up to 30 % by volume of hydrogen. It is preferable to use mixtures with a proportion of hydrogen of between 5 % by volume and 30% by volume, al- though it would also be possible within the scope of the invention to use mixtures with less than 5 % by weight.
  • carburizing gases endogas, methane, propane and such like
  • the proportion may be selected from a range with a lower limit of 0.01 % by volume and an upper limit of 2.55 % by volume by reference to the total mixture.
  • the temperatures during pre-sintering are between 740 and 1050°C and the sintering time may be between 10 minutes and 2 hours.
  • the objective of the pre-sintering process is to burn out the organic binding agents and lubricants and produce a light sintered bond between the particles.
  • the incomplete dissolution of individual alloy elements is deliberately obtained, thereby resulting in a lower hardness level.
  • the hardness of the sintered component is preferably set so that high degrees of formability with an extra factor of up to 30 % are possible during the subsequent compaction process (calibration). In particular, with a hardness of less than 140 HB 2.5/62.5, a surprisingly high formability was observed.
  • Oxygen-refined alloy elements in particular, such as Cr for example, are difficult to handle during pre-sintering.
  • a massive oxide formation during pre-sintering can be avoided, at least for the most part, so that this does not have a negative effect on formability.
  • pre-alloyed base powders containing Cr-Mo can also be calibrated because, due to the inadequate diffusion of the alloy elements and low cooling rates during pre-sintering, the structure is not able to harden or is so to only an inadequate degree. Cooling preferably takes place at a rate of a maximum of 2 K/min in the critical region of the material until the M f (Martensite Finish Temperature) is reached.
  • the powder grains are sintered to only a limited degree, which causes a weak sinter bonding.
  • the brown compacts are then compacted by means of coaxial pressing methods.
  • height changes of up to approximately 30% of the total component height can be re-shaped.
  • pressing pressures of up to 1400 MPa even higher die pressures are possible locally - a density increase to >7.35 g/cm 3 is achieved (lo- cally, higher densities are possible).
  • the lubricants which may optionally be used may be applied to the component either by conventional immersion methods or preferably by means of a spraying process before or during pressing.
  • the compacted brown compacts are sintered with a reducing atmosphere (nitrogen, hydrogen, as explained above) with the optional introduction of carburizing gases (endogas, methane, propane and such like), preferably in continuously operated sintering ovens.
  • a reducing atmosphere nitrogen, hydrogen, as explained above
  • carburizing gases endogas, methane, propane and such like
  • the temperatures during this high-temperature sintering may be between 1 100 °C and 1350°C.
  • the powder metal parts may be maintained at this temperature for between 10 minutes and 65 minutes.
  • the hardened parts are then cooled using appropriate cooling aggregates at the outlet of the oven at a cool- ing rate of between 2 K/s and 16 K/s from the sintering heat to below the M f and thus hardened.
  • the abrupt cooling and optionally the carburizing media during sintering result in the martensitic hardness structure and internal stresses, which are conducive to the mechanical properties and in particular to the fatigue properties.
  • the hardened parts may also be tempered.
  • the green compact, the brown compact or the finished sintered component may be subjected to mechanical processing of the type known from the prior art.
  • Example 1 sliding sleeve for an automotive transmission:
  • composition of the sinter powder Astaloy CrM (Cr-Mo-pre-alloyed Fe powder) + 0.4%C + 0.5% high-performance pressing agent
  • Proportion of carburizing gas in the high-temperature sintering atmosphere 0.05 %.
  • the finished sintered sleeve had a density of 7.4 g/cm 3 and compared with conventional sliding sleeves known from the prior art exhibited better resistance to wear during permanent service operation but also in the abuse test.
  • Example 2 sliding sleeve for an automotive transmission:
  • composition of the sinter powder Astaloy CrM (Cr-Mo-pre-alloyed Fe powder) + 0.4%C + 0.5% high-performance pressing agent
  • Proportion of carburizing gas in the high-temperature sintering atmosphere 0.1 %
  • the finished sintered sleeve had a density of 7.35 g/cm 3 and compared with conventional sliding sleeves known from the prior art exhibited a better resistance to wear during permanent service operation for the same abuse behaviour.
  • Example 3 coupling body for an automotive transmission:
  • composition of the sinter powder Astaloy CrM (Cr-Mo-pre-alloyed Fe powder) + 0.5%C + 0.5% high-performance pressing agent Pressing pressure to produce the green compact: 700 MPa (7.1 g/cm 3 density)
  • Proportion of carburizing gas in the high-temperature sintering atmosphere 0.1 %
  • the finished coupling body had a density of 7.38 g/cm 3 (with local densities in the region of the toothing >7.45g/cm 3 ) and compared with conventional coupling bodies known from the prior art exhibited a better resistance to wear.

Abstract

L'invention concerne un procédé de production d'une pièce en métal à base de poudre durcissable par frittage à partir d'une poudre de frittage contenant du chrome, comprenant les étapes consistant à préparer la poudre de frittage, comprimer la poudre de frittage pour former un comprimé cru, effectuer un pré-frittage du comprimé cru pour former un comprimé cuit sous une atmosphère réductrice suivi d'un lent refroidissement, calibrer le comprimé cuit et effectuer le frittage à haute température du comprimé cuit calibré suivi d'un refroidissement rapide. Le procédé de pré-frittage est effectué à une température sélectionnée dans une plage ayant une limite inférieure de 700 °C et une limite supérieure de 1050 °C.
EP08784503A 2007-09-03 2008-05-29 Procédé de production d'une pièce en métal à base de poudre durcissable par frittage Withdrawn EP2200770A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AT0137007A AT505698B1 (de) 2007-09-03 2007-09-03 Verfahren zur herstellung eines sinterhärtbaren sinterformteils
PCT/EP2008/004272 WO2009030291A1 (fr) 2007-09-03 2008-05-29 Procédé de production d'une pièce en métal à base de poudre durcissable par frittage

Publications (1)

Publication Number Publication Date
EP2200770A1 true EP2200770A1 (fr) 2010-06-30

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP08784503A Withdrawn EP2200770A1 (fr) 2007-09-03 2008-05-29 Procédé de production d'une pièce en métal à base de poudre durcissable par frittage

Country Status (3)

Country Link
EP (1) EP2200770A1 (fr)
AT (1) AT505698B1 (fr)
WO (1) WO2009030291A1 (fr)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU2011244998B2 (en) 2010-11-09 2016-01-14 Degudent Gmbh Method for the manufacture of a shaped body as well as green compact
JP5903738B2 (ja) * 2012-03-29 2016-04-13 住友電工焼結合金株式会社 鉄系焼結合金の製造方法
CN108526471B (zh) * 2018-06-11 2023-05-05 陕西华夏粉末冶金有限责任公司 一种铁基粉末冶金摩擦轮的制备方法
US11668298B2 (en) * 2018-11-07 2023-06-06 Hyundai Motor Company Slide of variable oil pump for vehicle and method of manufacturing the same
CN113843418A (zh) * 2021-09-28 2021-12-28 上海汽车变速器有限公司 一种汽车变速器信号轮的成型工艺

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Publication number Priority date Publication date Assignee Title
AU723317B2 (en) * 1996-05-13 2000-08-24 Gkn Sinter Metals Inc. Method for preparing high performance ferrous materials
US6126894A (en) * 1999-04-05 2000-10-03 Vladimir S. Moxson Method of producing high density sintered articles from iron-silicon alloys
US6338747B1 (en) * 2000-08-09 2002-01-15 Keystone Investment Corporation Method for producing powder metal materials
US7384445B2 (en) * 2004-04-21 2008-06-10 Höganäs Ab Sintered metal parts and method for the manufacturing thereof

Non-Patent Citations (2)

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Title
None *
See also references of WO2009030291A1 *

Also Published As

Publication number Publication date
WO2009030291A1 (fr) 2009-03-12
AT505698A1 (de) 2009-03-15
AT505698B1 (de) 2010-05-15

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