WO2013127905A1 - Composant d'automobile obtenu par la métallurgie des poudres et sa fabrication - Google Patents

Composant d'automobile obtenu par la métallurgie des poudres et sa fabrication Download PDF

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Publication number
WO2013127905A1
WO2013127905A1 PCT/EP2013/054005 EP2013054005W WO2013127905A1 WO 2013127905 A1 WO2013127905 A1 WO 2013127905A1 EP 2013054005 W EP2013054005 W EP 2013054005W WO 2013127905 A1 WO2013127905 A1 WO 2013127905A1
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WO
WIPO (PCT)
Prior art keywords
weight
component
sintered
iron
μιη
Prior art date
Application number
PCT/EP2013/054005
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English (en)
Inventor
Ulf Engström
Caroline Larsson
Original Assignee
Höganäs Ab (Publ)
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.)
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Application filed by Höganäs Ab (Publ) filed Critical Höganäs Ab (Publ)
Publication of WO2013127905A1 publication Critical patent/WO2013127905A1/fr

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Classifications

    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16H—GEARING
    • F16H55/00—Elements with teeth or friction surfaces for conveying motion; Worms, pulleys or sheaves for gearing mechanisms
    • F16H55/32—Friction members
    • F16H55/36—Pulleys
    • F16H55/48—Pulleys manufactured exclusively or in part of non-metallic material, e.g. plastics

Definitions

  • the present invention concerns a powder metallurgical produced component and the manufacturing process thereof.
  • the component is a belt pulley to be used in a combustion engine, the component having enhanced resistance against wear and sufficient strength.
  • the production method utilise comparably non expensive powder materials and production steps, hence being cost effective.
  • the sintered component contains a certain amount of pores decreasing the strength of the component.
  • the strength of the sintered component may be increased by introducing alloying elements such as carbon, copper, nickel, molybdenum etc.
  • the porosity of the sintered component may be reduced by increasing the compressibility of the powder composition, and/or increasing the compaction pressure for a higher green density, or increasing the shrinkage of the component during sintering. By locally eliminating the porosity where the presence of pores is most detrimental, i.e.
  • Automotive components of small and medium size are very suitable to be produced by the powder metallurgical route as these components often are made in large series and often have suitable geometries. Examples of such components are valve seats, cam lobes, connecting rods, sprockets, gears and belt pulleys.
  • valve seats cam lobes
  • connecting rods sprockets
  • gears gears and belt pulleys.
  • Belt pulleys are components which are produced today by the powder metallurgical production method and it should be possible to increase the production of automotive belt pulleys provided enough wear resistance could be obtained.
  • a problem with automotive belt pulleys is that when used in severe conditions where the engine is subjected to excessive dust or hard dust particles, particles may be trapped between the belt and the pulley causing wear on the pulley which may lead to slipping of the belt and possible severe damages on the motor. Such particles may also get into the surface pores where they may be stuck and causing excessive wear on the belt. Engines subjected to such conditions are therefore equipped with pulleys having high wear resistance and being produced by alternative methods to press and sintering. It would however be beneficial if the same type of cost effectively powder metallurgical produced pulleys could be used independently on the environmental conditions for the engine.
  • the present invention provides a solution to the problem described above.
  • inexpensive low chromium content and low molybdenum content prealloyed or admixed iron- based powders compacting such powders together with graphite and lubricants followed by sintering and a specific post- sinter heat treatment procedure, cost effective belt pulleys having improved wear resistance and sufficient mechanical strength can be obtained.
  • the heat treatment will also close the surface pores and hinder particle entrapment.
  • a method for producing a sintered and heat-treated component in particular a belt pulley, having enhanced wear resistance.
  • the method comprises the steps of; a) providing an iron based powder composition containing a prealloyed iron- based powder or an admixed iron- based powder, 0.20-0.90% by weight of graphite and, 0.20-1.5%) by weight of lubricant, the prealloyed iron- based powder or the admixed iron- based powder containing 1-3.5% by weight of chromium combined with 0.04-0.3 %, preferably 0.04-0.25%), by weight of manganese, inevitable impurities up to 1.0% and balance iron, b) compacting the iron- based powder composition into a green component having a density of 6.7-7.2 g/cm 3 , preferably 6.7-7.1 g/cm 3 , and most preferably 6.7-7.05 g/cm 3 c) sintering the green
  • the method comprises the steps of; a) providing an iron based powder composition containing a prealloyed iron- based powder or an admixed iron- based powder, 0.20-0.90% by weight of graphite and, 0.20-1.5%) by weight of lubricant, the prealloyed iron- based powder or the admixed iron- based powder containing 1 -3.5 % by weight of chromium, 0.15 - 1 % by weight of molybdenum, combined with 0.04-0.3%), preferably 0.04-0.25%), by weight of manganese, inevitable impurities up to 1.0% and balance iron, b) compacting the iron- based powder composition into a green component having a density of 6.7-7.2 g/cm 3 , preferably 6.7-7.1 g/cm 3 , and most preferably 6.7-7.05 g/cm 3 c) sintering the green component in a reducing atmosphere at a temperature between 1000°C and 1400°C for a
  • the iron- based powder used for producing the belt pulley may be produced through atomization of a melt containing the appropriate amount of chromium (Cr) and manganese (Mn), i.e. the alloying elements being present in pre- alloyed form. If higher strength of the core of the produced component is desired appropriate amount of molybdenum (Mo) may optionally be added to the melt.
  • the iron- based powder may be produced by admixing all or part of the alloying element(s) to an iron powder. Preferably the alloying elements being pre- alloyed.
  • the atomized powder is further subjected to a reduction annealing process.
  • the particle size of the steel powder could be any size as long as it is compatible with the press and sintering process. Examples of suitable particle size is the particle size of the known powder ABC 100.30 available from Hoganas AB, Sweden, having about 10% by weight above 150 um and about 20 % by weight below 45 ⁇ .
  • Cr serves to strengthen the matrix by solid solution hardening, Cr also increases hardenability. At the nitriding or nitrocarburizing processes Cr will form nitrides or nitrides and carbides enhancing oxidation resistance and abrasion resistance of the sintered body. A content of Cr above 3.5% by weight will however reduce the compressibility of the steel powder and render the formation of a desired
  • ferritic/pearlitic or pearlitic microstructure more difficult.
  • the content is below 3% by weight, even more preferred below 2% by weight.
  • Cr content below 1% by weight will have insignificant effect on desired properties.
  • Mo increases hardenability and strength.
  • Mo will as Cr form nitrides at the nitriding process.
  • Mo may be present in a content of 0.15-1%) by weight, preferably 0.2-0.6%) by weight.
  • a content of Mo less than 0.15% by weight will have insignificant effect on the properties and above 1% by weight the cost/effect ratio will become disadvantageous.
  • Mo may preferably be prealloyed as Mo has a very limited negative effect on compressibility. In some case it may be interesting to diffusion- bond some or all of the Mo content to the surface of the iron or iron- based powder. In such case lower amounts of Mo may be used. The reason being that the limited Mo content located in the particle boundary region contributes more to the hardenability than that in the matrix.
  • Mn will, as for chromium, increase the strength, hardness and hardenability. Content above 0.3% by weight will increase the risk of formation of manganese containing oxides and inclusions in the steel powder and will also have a negative effect on the compressibility due to solid solution hardening and increased ferrite hardness.
  • the manganese content is up to 0.25% by weight, even more preferably the manganese content is up to 0.2% by weight. If the manganese content is below 0.04% by weight it will not be possible to use recycled scrap unless a specific treatment for the reduction the Mn content during the course of the steel manufacturing is carried out.
  • Oxygen (O) is suitably at most 0.25% by weight to limit formation of oxides with chromium and manganese that impairs strength and compressibility of the powder. For these reasons oxygen preferably is at most 0.18% by weight.
  • Carbon (C ) in the steel powder shall be at most 0.1% by weight. Higher contents will unacceptably reduce the compressibility of the powder. For the same reason nitrogen shall be kept less than 0.1% by weight.
  • the total amount of inevitable impurities should be less than 1% by weight in order not to impair the compressibility of the steel powder or act as formers of detrimental inclusions.
  • Iron-based powder composition Before compaction the iron-based steel powder is mixed with graphite and lubricant(s). Graphite is added in an amount between 0.20-0.9% by weight of the composition and lubricant(s) are added in an amount between 0.2-1.5% by weight of the composition.
  • the iron-base powder composition can also be prepared as a "bonded mix" where finer particles in the iron- based powder composition are adhered to the larger particles by means of a binder.
  • carbon is introduced in the matrix.
  • Carbon is added as graphite in amount between 0.20-0.9% by weight of the composition. An amount less than 0.20% by weight will result in too low hardness and strength and an amount above 0.9% will result in an excessive formation of carbides yielding too high hardness, insufficient elongation and impair the
  • Lubricant(s) are added to the composition in order to facilitate compaction of the composition and ejection of the compacted component.
  • the addition of less than 0.20% by weight of the composition will have insignificant effect and the addition of above 1.5% by weight of the composition will result in too low density of the compacted body.
  • Lubricants may be chosen from the group of metal stearates, waxes, fatty acids and derivates thereof, oligomers, polymers and other organic substances having lubricating effect.
  • hard phase materials and machinability enhancing agents such as MnS, MoS 2 , CaF 2 , bentonites and other kinds of minerals etc. may be added at an amount of 0.1-1%> by weight of the iron- based powder composition.
  • the iron-based powder composition is transferred into a mould and subjected to a compaction pressure of about 400-1300 MPa to a green density between 6.7 and 7.2 g/cm 3 , preferably between 6.7 and 7.1 g/cm 3 , and most preferably between 6.7 and 7.05 g/cm 3 .
  • the obtained green component is further subjected to sintering in a reducing atmosphere at a temperature of about 1000-1400° C, preferably between about 1100- 1300° C
  • Sintering is followed by a steam treatment process in order to close the porosity and improve the wear resistance.
  • the closure of the porosity at the surface is also beneficial for the ability of controlling the formation of the nitride containing compound layer.
  • an oxide layer mainly free from surface pores, is created having a thickness of 5-15 ⁇ , preferably 5-10 ⁇ .
  • the steam treatment process may be performed by subjecting sintered component to steam at atmospheric pressure or above at a temperature between 400°C and 570°C, preferably 500°C -550°C, most preferably 500°C -520°C for a period between 30 minutes and 4 hours, preferably for a period between 60 minutes and 1.5 hours.
  • the component is subjected to a to a nitriding step in an atmosphere containing nitrogen.
  • the nitriding step is performed at a temperature between 460°C and 550°C, preferably between 470°C and 490°C for a period of 15 minutes to 5 hours, preferably 30 minutes to 1.5 hours.
  • the steam treated component is subjected to a nitrocarburizing step in an atmosphere containing nitrogen and carbon.
  • the nitrocarburizing step is performed at a temperature between 525 °C and 625°C, preferably between 550°C and 590°C, more preferably between 570°C and 590°C for a period of 15 minutes to 4 hours, preferably 30 minutes to 1.5 hours.
  • Nitriding or nitrocarburizing are classified as low temperature heat treatments in contrast to case hardening which is performed at higher temperatures above 850°C. By performing the heat treatments at low temperatures less dimensional change and distortion of the heat treated body will occur, compared to case hardening, as the material is not subjected to phase transformations.
  • the oxide layer is gradually reduced and transformed into a compound layer containing Cr- or Cr-Mo- containing nitrides and carbides.
  • the process for formation of the compound layer is stopped before the entire oxide layer at the surface of the component has been reduced and transformed into a compound layer, thus a component having remaining layer of oxides combined with a compound layer is obtained.
  • all oxides at the surface are reduced and transformed into the compound layer.
  • the nitriding or nitrocarburizing processing is controlled through adjusting temperature and/or nitriding or nitrocarburizing time and /or the composition of the nitriding or nitrocarburizing atmosphere in order to obtain a compound layer having a thickness of 1-25 ⁇ , preferably 5-20 ⁇ , more preferably 5-15 ⁇ and even more preferably 8-13 ⁇ .
  • a too thick compound layer increases the risk of peeling, whereas a compound layer thinner than 5 ⁇ and definitely thinner than 1 ⁇ will probably render the component insufficient wear properties.
  • the hardness of the compound layer is above 700 mhv (microvikers) measured on the component surface. Beneath the compound layer a diffusion zone is obtained giving a good support to the surface layer(s).
  • the hardness of this diffusion layer is above 500 mhv and preferably above 550 and most preferably 600 mvh just below the compound layer and decreased gradually to the centre.
  • the hardening depth, where the hardness is 450 mhv, shall be between 200-700 ⁇ from the surface.
  • the hardness of the core is mainly determined by the carbon content of the material.
  • the hardness of the core should however be below 400 mhv, preferably below 350 mhv in order to render the core enough ductility.
  • a sintered and heat-treated component in particular a belt pulley, having enhanced wear resistance.
  • the density of the sintered component shall be between 6.7 and 7.2 g/cm 3 , preferably between 6.7 and 7.1 g/cm 3 , and most preferably between 6.7 and 7.05 g/cm 3 .
  • a sintered density above 7.2 g/cm 3 may be beneficial in terms of strength and ductility of the component such density it is not regarded as cost effective for applications which the present invention is directed to, i.e. components subjected to wear from hard dust particles, e.g. belt pulleys.
  • the inter component variation in sintered density shall be at most 0.4 g/cm 3 , preferably at most 0.3 g/cm 3 and most preferably at most 0.2 g/cm 3 . If this variation is too high the different layers will not be uniformly formed and have an unacceptable variation in thickness leading to an unacceptable variation in hardness profile.
  • the component is further characterised by;
  • pearlitic and/or bainitic microstructure having a pearlitic and/or bainitic microstructure, alternatively pearlitic and/or bainitic microstructure combined with ferrite, and at least one specified wear resistant surface layer and a diffusion zone,
  • the balance being iron and inevitable impurities up to 1.0% by weight, -the wear resistant surface layer(s) consisting of;
  • an oxide layer having a thickness of 0-15 ⁇ , preferably 0-10 ⁇ , more preferably 0-5 ⁇ ,
  • a compound layer having a thickness of 1-25 ⁇ , preferably 5-20 ⁇ , more preferably 5-15 ⁇ , and containing nitrides or nitrides and carbides of Cr,
  • the diffusion zone having hardness above 500 mhv, preferably above 550 mhv and most preferable above 600 mvh just below the compound layer and decreasing gradually towards the centre.
  • the hardening depth or hardness profile shall be 450 mvh at a depth between 200 and 700 ⁇ from the surface.
  • the Cr content is limited to 1-3%, preferably 1-2%) by weight.
  • the Mn content is limited to 0.04-0.25% or preferably 0.04-0.2% by weight.
  • the oxide layer is excluded, hence wear resistance is solely provided by the compound layer and diffusion layer.
  • the component is further characterised by;
  • pearlitic and/or bainitic microstructure having a pearlitic and/or bainitic microstructure, alternatively pearlitic and/or bainitic microstructure combined with ferrite, and at least one specified wear resistant surface layer and a diffusion zone,
  • the balance being iron and inevitable impurities up to 1.0 % by weight, -the wear resistant surface layer(s) consisting of;
  • an oxide layer having a thickness of 0-15 ⁇ , preferably 0-10 ⁇ , more preferably 0-5 ⁇ ,
  • a compound layer having a thickness of 1-25 ⁇ , preferably 5-20 ⁇ , more preferably 5-15 ⁇ , and containing nitrides or nitrides and carbides of Cr and Mo,
  • the diffusion zone having hardness above 500 mhv, preferably above 550 mhv and most preferable above 600 mvh just below the compound layer and decreasing gradually towards the centre.
  • the hardening depth or hardness profile shall be 450 mvh at a depth between 200 and 700 ⁇ from the surface.
  • the Cr content is limited to 1-3%, preferably 1-2%) by weight. In specific embodiments of the invention the Mo content is limited to 0.2-0.6% by weight.
  • the Mn content is limited to 0.04-0.25% or preferably 0.04-0.2%> by weight.
  • the oxide layer is excluded, hence wear resistance is solely provided by the compound layer and diffusion layer.
  • the obtained iron- based powder composition was further compacted into test samples having a diameter of 65 mm and height of 32 mm to a density of 6.9 g/cm 3 .
  • the green samples were thereafter sintered in an atmosphere of 90 % nitrogen gas/ 10 % hydrogen gas at 1120°C for 30 minutes.
  • the sintering step was followed by steam treatment in a water vapour containing atmosphere at 510°C for 90 minutes.
  • Samples were cross sectioned for metallographic examination.
  • the examination of the sample according to the invention reveals an oxide layer having a thickness of 2-3 ⁇ , a compound layer having a thickness of 10-15 ⁇ and a diffusion zone beneath the compound layer.
  • Figure 1 shows the cross section of the sample according to the invention revealing the well-defined coherent wear resistant surface layers without any surface porosity. Microvickers hardness, mhv, HVo.i , was determined according to ISO 6507-1 at various depths from the surface. The results are shown in figure 3.
  • 650-600 HVo.i was measured at a position just below the compound layer, and the case depth with a hardness higher than 450 HVo.i was in the range of 500 mm.
  • Figure 2 shows the cross section of the comparative example. The figure showing less well-defined surface layer having varying depth and some surface pores. Microvickers hardness for the comparative example was measured to 300-350 HVo.i at a position just below the surface.
  • Figure 2 also shows the compound layer formed as a network in the grain boundaries as well as on the surfaces off the inner pores which may cause brittleness.
  • the cross section of the sample according to the invention exhibits a well-defined compound layer and a relatively thick diffusion zone having higher hardness.

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

Abstract

La présente invention concerne un composant produit par la métallurgie des poudres et son procédé de fabrication. En particulier, le composant est une poulie à courroie qui doit être utilisée dans un moteur à combustion, le composant ayant une meilleure résistance à l'usure et une résistance mécanique suffisante. Le procédé de fabrication utilise des matières en poudre et des étapes de production relativement peu coûteuses, de telle sorte qu'il est économique.
PCT/EP2013/054005 2012-02-29 2013-02-28 Composant d'automobile obtenu par la métallurgie des poudres et sa fabrication WO2013127905A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP12157563 2012-02-29
EP12157563.3 2012-02-29

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WO2013127905A1 true WO2013127905A1 (fr) 2013-09-06

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104712512A (zh) * 2013-12-16 2015-06-17 罗伯特·博世有限公司 具有磨损保护层的、流体静力的轴向活塞机的滚筒
EP3050692A1 (fr) * 2015-01-28 2016-08-03 Steering Solutions IP Holding Corporation Moyeu de poudre métallique et traitement
CN108223762A (zh) * 2016-12-21 2018-06-29 湖北浙峰源商贸有限公司 一种长寿命皮带轮及其表面强化处理工艺
CN109128183A (zh) * 2018-08-07 2019-01-04 东睦新材料集团股份有限公司 一种铁基粉末冶金零件的制造方法
WO2019047031A1 (fr) * 2017-09-05 2019-03-14 戴文凤 Procédé de métallurgie des poudres pour poulies à courroie
CN110666177A (zh) * 2019-10-21 2020-01-10 安阳工学院 一种多层纳米晶复合结构NiCrAlBNb基轴承保持架材料及其制备方法
CN111842901A (zh) * 2020-08-12 2020-10-30 泰安皆瑞金属科技有限公司 一种适用于vvt发动机皮带轮的粉末冶金加工工艺

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5383979A (en) * 1991-02-07 1995-01-24 Robert Bosch Gmbh Process for producing a surface-hardened workpiece from sintered iron
US20070283778A1 (en) * 2006-03-29 2007-12-13 Hitachi Powdered Metals Co., Ltd. Sintered gear and production method therefor
WO2011152774A1 (fr) * 2010-06-04 2011-12-08 Höganäs Ab (Publ) Aciers frittés nitrurés

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5383979A (en) * 1991-02-07 1995-01-24 Robert Bosch Gmbh Process for producing a surface-hardened workpiece from sintered iron
US20070283778A1 (en) * 2006-03-29 2007-12-13 Hitachi Powdered Metals Co., Ltd. Sintered gear and production method therefor
WO2011152774A1 (fr) * 2010-06-04 2011-12-08 Höganäs Ab (Publ) Aciers frittés nitrurés

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104712512A (zh) * 2013-12-16 2015-06-17 罗伯特·博世有限公司 具有磨损保护层的、流体静力的轴向活塞机的滚筒
EP3050692A1 (fr) * 2015-01-28 2016-08-03 Steering Solutions IP Holding Corporation Moyeu de poudre métallique et traitement
CN105889460A (zh) * 2015-01-28 2016-08-24 操纵技术Ip控股公司 粉末金属毂和处理
US9759304B2 (en) 2015-01-28 2017-09-12 Steering Solutions Ip Holding Corporation Powder metal hub and treatment
CN105889460B (zh) * 2015-01-28 2018-12-25 操纵技术Ip控股公司 粉末金属毂和处理
CN108223762A (zh) * 2016-12-21 2018-06-29 湖北浙峰源商贸有限公司 一种长寿命皮带轮及其表面强化处理工艺
WO2019047031A1 (fr) * 2017-09-05 2019-03-14 戴文凤 Procédé de métallurgie des poudres pour poulies à courroie
CN109128183A (zh) * 2018-08-07 2019-01-04 东睦新材料集团股份有限公司 一种铁基粉末冶金零件的制造方法
CN109128183B (zh) * 2018-08-07 2020-12-22 东睦新材料集团股份有限公司 一种铁基粉末冶金零件的制造方法
CN110666177A (zh) * 2019-10-21 2020-01-10 安阳工学院 一种多层纳米晶复合结构NiCrAlBNb基轴承保持架材料及其制备方法
CN111842901A (zh) * 2020-08-12 2020-10-30 泰安皆瑞金属科技有限公司 一种适用于vvt发动机皮带轮的粉末冶金加工工艺

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