• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    An Fe-Mo-Cu-C-based alloy steel powder for powder metallurgy has a chemical composition containing Mo: 0.2 mass% to 1.5 mass%, Cu: 0.5 mass% to 4.0 mass%, and C: 0.1 mass% to 1.0 mass%, with a balance being Fe and incidental impurities, wherein an iron-based powder has a mean particle size of 30 urn to 120 urn, and a Cu powder has a mean particle size of 25 urn or less. Despite the alloy steel powder for powder metallurgy having a chemical composition not containing Ni, a part produced by sintering a press formed part of the powder and further carburizing-quenching-tempering the sintered part has mechanical properties of at least as high tensile strength, toughness, and sintered density as a Ni-added part.
    公开号:SE1750649A1
    申请号:SE1750649
    申请日:2015-11-24
    公开日:2017-05-24
    发明作者:Takashita Takuya；Kobayashi Akio；Nakamura Naomichi；Maetani Toshio；Sonobe Akio；SATO Itsuya
    申请人:Jfe Steel Corp；
    IPC主号:
    专利说明:

    [1] [0001] The disclosure relates to an alloy steel powder for powder metallurgyincluding a partial diffusion alloy steel powder and not containing Ni, whichis suitable for the production of high strength sintered parts for vehicles.The disclosure also relates to an alloy steel powder for powder metallurgy thateasily increases in sintered density when sintered and achieves higher tensilestrength, toughness (impact value), and fatigue strength aftercarburizing-quenching-tempering processes than conventional alloy steelpowders.
    [2] [0002] Powder metallurgical techniques enable producing parts havingcomplicated shapes in shapes (i.e. near net shapes) extremely close to productshapes, with high dimensional accuracy. The use of powder metallurgicaltechniques in producing parts therefore contributes to significantly lowermachining costs. For this reason, powder metallurgical products obtained bypowder metallurgical techniques have been used as various mechanical partsin many fields.
    [3] [0003] Powder metallurgical techniques mainly use iron-based powders.Iron-based powders are categorized into iron powder (e.g. pure iron powder),alloy steel powder, and the like, depending on the components. Iron-basedpowders are also categorized into atomized iron powder, reduced iron powder,and the like, depending on the production method. In the case of using thecategories by the production method, the term “iron powder” has a broadmeaning encompassing not only pure iron powder but also alloy steel powder.[0004] Such an iron-based powder is used to produce a green compact. A green compact is typically produced by mixing an iron-based powder with POl53453-PCT-ZZ (l/26) alloying powders such as a Cu powder and a graphite powder and a lubricantsuch as stearic acid or lithium stearate to obtain an iron-based mixed powder,and then charging the iron-based mixed powder into a die and pressing it.[0005] The density of a green compact obtained by a typical powdermetallurgy process is normally about 6.6 Mg/ms to 7.1 Mg/mg. The greencompact is then sintered to form a sintered body. The sintered body isfurther subjected to optional sizing and machining work to form a powdermetallurgical product.
    [6] [0006] Increases in strength of powder metallurgical products have beenstrongly requested recently, for reductions in size and weight of parts. Therehas been particularly strong demand for strengthening iron-based powderproducts (iron-based sintered bodies) made from iron-based powders.
    [7] [0007] Known examples of an iron-based powder as a powder with alloyingelements added thereto at the stage of a precursor powder include: (l) a mixedpowder obtained by adding each alloying element powder to a pure ironpowder; (2) a pre-alloyed steel powder obtained by completely alloying eachelement; and (3) a partial diffusion alloy steel powder (also referred to as“composite alloy steel powder”) obtained by partially diffusionally adheringeach alloying element powder to the surface of a pure iron powder orpre-alloyed steel powder.
    [8] [0008] The mixed powder (l) obtained by adding each alloying elementpowder to a pure iron powder is advantageous in that high compressibilityequivalent to that of a pure iron powder is ensured.
    [10] [0010] The partial diffusion alloy steel powder (3) is produced by addingeach metal powder to a pure iron powder or a pre-alloyed steel powder andheating the resultant powder in a non-oxidizing or reducing atmosphere topartially diffusionally bond the metal powder to the surface of the pure ironpowder or pre-alloyed steel powder. This partial diffusion alloy steel powdercombines the advantages of the iron-based mixed powder (1) and pre-alloyedsteel powder (2), while avoiding various problems seen in the iron-basedmixed powder (1) and the pre-alloyed steel powder (2).
    [11] [0011] In detail, the partial diffusion alloy steel powder (3) ensures loweroxygen content in the sintered body and high compressibility equivalent tothat of a pure iron powder. Moreover, since a multi-phase made up of acomplete alloy phase and a partially concentrated phase is formed, the matrixcan be strengthened. The partial diffusion alloy steel powder has thereforebeen widely developed as it can cope with the recent requests forstrengthening parts.
    [12] [0012] Basic alloy components used in the partial diffusion alloy steelpowder include Ni and Mo.
    [13] [0013] Mo has an effect of increasing hardenability, and so suppresses theformation of ferrite during quenching and facilitates the formation of bainiteor martensite in the metallic microstructure. By this effect, Mo not only transformation-strengthens the matrix phase, but alsosolid-solution-strengthening the matrix phase by dispersing in the matrixphase, and forms fine carbide in the matrix phase to strengthen the matrixphase by precipitation. Mo also has good gas carburizing property and is anon-grain boundary oxidizable element, and so can strengthen the sinteredbody by carburizing.
    [14] [0014] As an example of a mixed powder for high strength sintered parts using a partial diffusion alloy steel powder containing these alloy components,JP 3663929 B (PTL 1) describes a mixed powder for high strength sinteredparts obtained by mixing an alloy steel powder formed by partially alloying Ni: 0.5 mass% to 4 mass% and Mo: 0.5 mass% to 5 mass% with Ni: 1 mass% to 5 mass%, Cu: 0.5 mass% to 4 mass%, and a graphite powder: 0.2 mass% to 0.9 mass%.
    [15] [0015] As an example of an iron-based sintered body having high density andnot containing Ni, JP H4-285141 A (PTL 2) describes a method of producing an iron-based sintered body by mixing an iron-based powder of 1 um to 18 umin mean particle size with a Cu powder of 1 um to 18 um in mean particle size at a weight ratio of l00:(0.2 to 5) and forming and sintering the mixedpowder.
    [16] [0016] This technique uses an iron-based powder having an extremely smallermean particle size than a typical iron-based powder, and thus achieves a high sintered body density of 7.42 g/cms or more which is normally impossible.
    [17] [0017] PTL 1: JP 3663929 BPTL 2: JP H4-285141 A POl53453-PCT-ZZ (4/26) SUMMARY(Technical Problem)[0018] However, we found out as a result of study that a sintered materialproduced using the mixed powder described in PTL 1 and a sintered materialproduced by the method described in PTL 2 have the following problems.
    [19] [0019] A larger amount of Ni is likely to be needed in the case of obtaining ahigh strength material of 1000 MPa or more using the mixed powder describedin PTL l.
    [20] [0020] Besides, the use of Ni as an alloying element requires prolongedsintering in order to sufficiently diffuse Ni in the iron powder or steel powder.Brief sintering causes non-uniform metallic microstructure.
    [21] [0021] The sintered material produced by the method described in PTL 2contains no Ni, but the mean particle size of the iron-based powder used is 1um to 18 um which is smaller than normal. Such a small particle size causeslower powder fluidity, and degrades the die filling ability of the powder.This leads to very poor work efficiency during press forming.
    [22] [0022] In recent years, various parts have been required to have high fatiguestrength for improved safety. The aforementioned conventional techniques,however, have difficulty in achieving high fatigue strength.
    [23] [0023] It could be helpful to provide an alloy steel powder for powdermetallurgy having the following features, together with a sintered bodyproduced using the alloy steel powder.
    [24] [0024] We conducted various studies on alloy components of an alloy steelpowder for powder metallurgy not containing Ni and means for adding thealloy components. As a result, we discovered the following.
    [25] [0025] Mo functions as a ferrite-stabilizing element during sintering heattreatment. Hence, ferrite phase forms in a portion having a large amount ofMo and its vicinity and the sintering ofthe iron powder progresses, as a resultof which the sintered body increases in sintered density.
    [26] [0026] Meanwhile, Cu melts and permeates between the particles of the ironpowder during sintering, and increases the distance between the particles ofthe iron powder. This causes Cu expansion, that is, the size of the sinteredbody being larger than the size of the green compact. When the Cuexpansion occurs, the sintered body density decreases. A significantdecrease in density caused by the Cu expansion leads to drawbacks such aslower strength and toughness of the sintered body.
    [27] [0027] We accordingly conducted intensive study on the characteristics oftheCu powder used. As a result, we discovered that, by limiting the Cu powderto a specific shape, the Cu expansion was reduced, and not only a decrease insintered body density was suppressed but also the sintered body densityincreased in some cases.
    [28] [0028] We also discovered that simultaneously controlling the mean particle size of the iron-based powder used to 30 um or more improved the fluidity of POl53453-PCT-ZZ (6/26) the alloy steel powder, and the use of an iron-based powder produced by anatomizing method increased the fatigue strength ofthe sintered body.
    [29] [0029] In detail, we provide the following. 1. An Fe-Mo-Cu-C-based alloy steel powder for powder metallurgy,comprising: a partial diffusion alloy steel powder obtained by diffusionallyadhering Mo to an iron-based powder; a Cu powder; and a graphite powder,wherein the alloy steel powder for powder metallurgy has a chemicalcomposition containing (consisting of) Mo: 0.2 mass% to 1.5 mass%, Cu: 0.5mass% to 4.0 mass%, and C: 0.1 mass% to 1.0 mass%, with a balance being Feand incidental impurities, and the iron-based powder has a mean particle sizeof 30 um to 120 um, and the Cu powder has a mean particle size of 25 um orless.
    [30] [0030] 2. An Fe-Mo-Cu-C-based alloy steel powder for powder metallurgy,comprising: a partial diffusion alloy steel powder obtained by diffusionallyadhering Mo to an iron-based powder; a Cu powder; and a graphite powder,wherein the alloy steel powder for powder metallurgy has a chemicalcomposition containing Mo: 0.2 mass% to 1.5 mass%, Cu: 0.5 mass% to 4.0mass%, and C: 0.1 mass% to 1.0 mass%, with a balance being Fe andincidental impurities, and the iron-based powder has a mean particle size of30 um to 120 um, and the Cu powder has a flat shape and satisfies a relation LS -2d + 50 where d is a thickness of the Cu powder in um and L is a diameterin a major axis ofthe Cu powder in um.
    [31] [0031] 3. An Fe-Mo-Cu-C-based alloy steel powder for powder metallurgy,comprising: a partial diffusion alloy steel powder obtained by diffusionallyadhering Mo to an iron-based powder; a Cu powder; and a graphite powder,wherein the alloy steel powder for powder metallurgy has a chemicalcomposition containing Mo: 0.2 mass% to 1.5 mass%, Cu: 0.5 mass% to 4.0mass%, and C: 0.1 mass% to 1.0 mass%, with a balance being Fe andincidental impurities, and the iron-based powder has a mean particle size of30 um to 120 um, and the Cu powder is a mixed powder of a Cu powderhaving a mean particle size of 25 um or less and a Cu powder having a flatshape and satisfying a relation L S -2d + 50 where d is a thickness of the Cu powder in um and L is a diameter in a major axis of the Cu powder in um.
    [32] [0032] 4. A sintered body produced using the alloy steel powder for powdern1etallurgy according to any one of l. to 3.
    [33] [0033] It is thus possible to obtain an alloy steel powder for powdern1etallurgy that, despite having a chen1ical con1position not containing Ni,enables the production of a sintered body having niechanical properties of atleast as high tensile strength, toughness, and fatigue strength as a Ni-addedpart and also having high sintered density.
    [36] [0036] A sintered body according to the en1bodin1ent is produced bysubjecting the alloy steel powder for powder n1etallurgy to conventional pressforn1ing to obtain a green compact and further subjecting the green con1pact to conventional sintering.
    [37] [0037] If the sintered body density increases, both the strength and toughnessof the sintered body increase. Unlike a conventional sintered body producedusing Ni, the sintered body according to the embodiment has uniform metallicmicrostructure and so exhibits mechanical properties with little Variation instrength or toughness.
    [38] [0038] The reasons for the limitations in the embodiment are described below.In the following description, “%” denotes mass%, and the amount of Mo, theamount of Cu, and the amount of graphite powder each denote the contentratio to the alloy steel powder for powder metallurgy.
    [39] [0039] The iron-based powder used in the embodiment is described first.
    [40] [0040] Examples ofthe iron-based powder include an as-atomized powder, anatomized iron powder, and a reduced iron powder. The iron-based powder used in the embodiment is preferably an iron-based powder produced by an POl53453-PCT-ZZ (9/26) _10- atomizing method, that is, an as-atomized powder and/or an atomized ironpowder.
    [41] [0041] Thus, the iron-based powder used in the embodiment may be any of:an as-atomized powder obtained by atomizing molten steel and then dryingand classifying the resulting powder without heat treatment for deoxidation(reduction), decarburization, or the like; and an atomized iron powderobtained by reducing an as-atomized powder in a reducing atmosphere.
    [42] [0042] The following describes Mo used in the embodiment.
    [43] [0043] As a Mo material powder, a Mo-containing powder itself may be used,or a Mo compound that can be reduced to a Mo-containing powder may beused. As the Mo-containing powder, a pure metal powder of Mo, an oxidizedMo powder, an Fe-Mo (ferromolybdenum) powder, or the like is advantageous.As the Mo compound, Mo carbide, Mo sulfide, Mo nitride, or the like issuitable.
    [44] [0044] The iron-based powder and the Mo material powder are mixed so that POl53453-PCT-ZZ (l 0/26) _11- the amount of M0 is in the range of 0.2% to 1.5% with respect to the alloysteel powder for powder metallurgy. The mixing method is not particularlylimited, and may be a conventional method using a Henschel mixer, a conemixer or the like.
    [45] [0045] The mixed powder (the iron-based powder + the Mo material powder)is then held at a high temperature, and subjected to heat treatment ofdiffusionally bonding Mo to iron in the contact surface of the iron-basedpowder and the Mo material powder, to obtain a partial alloy steel powder ofMo.
    [47] [0047] The balance of the partial alloy steel powder is iron and incidentalimpurities in the embodiment. Examples of the impurities contained in thepartial alloy steel powder include C, O, N, and S. As long as the contents ofthese components are limited to C: 0.02% or less, O: 0.3% or less, N: 0.004%or less, and S: 0.03% or less with respect to the partial alloy steel powder, there is no particular problem. The O content is more preferably 0.25% or POl53453-PCT-ZZ (11/26) _12- less. If the contents of the incidental impurities exceed these ranges, thepartial alloy steel powder decreases in compressibility, and is difficult to becompression molded into a preformed body having sufficient density.
    [48] [0048] In the embodiment, a Cu powder and a graphite powder (a carbonpowder such as graphite) are added to the partial alloy steel powder obtainedas described above, in order to achieve a tensile strength of 1000 MPa or moreafter carburizing-quenching-tempering the sintered body.
    [49] [0049] The following describes the Cu powder used in the embodiment.
    [50] [0050] The median size can be determined by the following method.
    [51] [0051] The type distribution measurement device applies laser light to a solvent in which the Cu powder is laser diffraction-scattering particle size POl53453-PCT-ZZ (12/26) _13- dispersed, and measures the particle size distribution and mean particle size ofthe Cu powder from the diffraction and scattering strength of the laser light.The solvent in which the Cu powder is dispersed is preferably ethanol whichhas good particle dispersibility and is easy to handle. The use of a solventwith a high van der Waals force and low dispersibility, such as water, is notpreferable because particles coagulate during the measurement and themeasurement result is coarser than the actual mean particle size.
    [52] [0052] The ethanol solution into which the Cu powder is charged ispreferably ultrasonic treatment before the subjected to dispersion measurement. Since the appropriate dispersion treatment time differsdepending on the powder to be measured, the measurement is performedseveral times while varying the dispersion treatment time in the range of 0minutes to 60 minutes.
    [53] [0053] - The Cu powder having a flat shape and satisfying the relation L S -2d+ 50 where d (um) is the thickness of the Cu powder and L (um) is thediameter in the major axis of the Cu powder The Cu powder can suppress the aforementioned decrease in sinteredbody density even when its mean particle size is more than 25 um, as long asthe Cu powder has a predetermined flat shape. In this case, the Cu powdersatisfies the relation L S -2d + 50 where d (um) is the thickness ofthe powderand L (um) is the diameter in the major axis of the powder. The lower limitof d is not particularly limited, but is preferably about 0.05 um to avoid anunnecessary increase ofthe Cu powder production cost. The upper limit of dis not particularly limited, but is preferably about 12.5 um.
    [54] [0054] The flat powder in the embodiment is a powder that satisfies therelation L S -2d + 50, and is made up of flat particles whose diameter (length)in the thickness direction (the direction perpendicular to the plane with thesmallest flattening (highest roundness), the direction of reference sign 2 inFIG. l) is smaller than the diameter in the spreading direction (the direction of the plane with the smallest flattening, the direction of reference sign l in FIG.
    [56] [0056] By limiting the Cu powder to the aforementioned shape, Cu expansionis suppressed, and the decrease in sintered body density is reduced, or ratherthe sintered body density increases.
    [57] [0057] A mixed Cu powder obtained by mixing the aforementioned Cupowder having a mean particle size of 25 um or less and the aforementionedCu powder having the predetermined flat shape, i.e. satisfying the relation L S-2d + 50, may be used in the embodiment. The mixture ratio of the Cupowders of the respective shapes in the mixed Cu powder is not particularlylimited.
    [58] [0058] - The additive amount ofthe Cu powder: 0.5% to 4.0% If the additive amount of the Cu powder is less than 0.5%, theaforementioned advantageous effect of the Cu addition cannot be achieved.If the additive amount ofthe Cu powder is more than 4.0%, not only the effectof increasing the strength of the sintered part is saturated, but also the effectof the Cu powder shape decreases, leading to a decrease in sintered bodydensity. The additive amount of the Cu powder is therefore limited to therange of 0.5% to 4.0%.in the range of l.0% to 30%.
    [59] [0059] The following describes the graphite powder used in the embodiment.
    [61] [0061] In the case where the part needs to be further shaped by machiningwork or the like at the sintered body stage, powders for improvingmachinability such as MnS may be added as appropriate according to aconventional method.
    [62] [0062] The following describes suitable pressing conditions and sinteringconditions for producing the sintered body using the alloy steel powder forpowder metallurgy according to the embodiment.
    [64] [0064] The green compact is sintered preferably in the temperature range of1100 °C to 1300 °C. sintering does not progress, and a desired tensile strength (1000 MPa or more) If the sintering temperature is less than 1100 °C, the If the sintering temperature is more than 1300 °C, the life ofThe is not obtained.the sintering furnace shortens, which is economically disadvantageous.sintering time is preferably in the range of 10 minutes to 180 minutes.[0065] The sintered body produced by the aforementioned procedure usingthe alloy steel powder according to the embodiment has higher sintered bodydensity than a sintered body produced from a green compact ofthe same greendensity by a conventional production method.
    [66] [0066] The strengthening treatment such as carburizing-quenching, bright quenching, obtained sintered body may be optionally subjected to induction hardening, and carburizing nitriding treatment. Even in the casewhere such strengthening treatment is not performed, the sintered bodyproduced using the alloy steel powder for powder metallurgy according to thecompared with Each embodiment has improved strength and toughness asconventional sintered bodies not subjected to strengthening treatment.strengthening treatment may be performed according to a conventional method.
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    [69] [0069] As shown in Table l, in all Examples, despite the alloy steel powderfor powder metallurgy having a chemical composition not containing Ni, apart produced using the powder as a precursor powder had mechanicalproperties of at least as high tensile strength and toughness as a Ni-addedmaterial.
    Table l 4Ni(4%Ni-l.5%Cu-0.5%Mo partial alloy steel powder obtained by adding a Ni also shows the results of a materialpowder (mean particle size: 8 pm), an oxidized Mo powder (mean particlesize: l0 pm), and a Cu powder (mean particle size: 28 pm) to an iron-basedpowder (as-atomized powder, apparent density: 2.80 Mg/mg, mean particlesize: 65 pm), mixing them, and heat treating the mixed powder todiffusionally adhere Ni, Mo, and Cu to the surface of the iron-based powder),as Conventional Example.
    In Examples, a sintered body (iron-based sintered body) having highdensity and also having both high strength and high toughness was obtainedeven by a typical sintering method.
    Moreover, in Examples, the alloy steel powder had excellent fluidity.
    REFERENCE SIGNS LIST[0070] l2 thickness: d diameter in major axis: L Ref. No. POl53453-PCT-ZZ (23/26)
    权利要求:
    Claims (4)
    [1] 1. An Fe-Mo-Cu-C-based alloy steel powder for powdermetallurgy, comprising: a partial diffusion alloy steel powder obtained by diffusionallyadhering Mo to an iron-based powder; a Cu powder; and a graphite powder, wherein the alloy steel powder for powder metallurgy has a chemicalcomposition containing Mo: 0.2 mass% to 1.5 mass%, Cu: 0.5 mass% to 4.0mass%, and C: 0.1 mass% to 1.0 mass%, with a balance being Fe andincidental impurities, and the iron-based powder has a mean particle size of 30 um to 120 um,and the Cu powder has a mean particle size of 25 um or less.
    [2] 2. An Fe-Mo-Cu-C-based alloy steel powder for powdermetallurgy, comprising: a partial diffusion alloy steel powder obtained by diffusionallyadhering Mo to an iron-based powder; a Cu powder; and a graphite powder, wherein the alloy steel powder for powder metallurgy has a chemicalcomposition containing Mo: 0.2 mass% to 1.5 mass%, Cu: 0.5 mass% to 4.0mass%, and C: 0.1 mass% to 1.0 mass%, with a balance being Fe andincidental impurities, and the iron-based powder has a mean particle size of 30 um to 120 um,and the Cu powder has a flat shape and satisfies a relation L S -2d + 50 whered is a thickness ofthe Cu powder in um and L is a diameter in a major axis ofthe Cu powder in um.
    [3] 3. An Fe-Mo-Cu-C-based alloy steel powder for powdermetallurgy, comprising: a partial diffusion alloy steel powder obtained by diffusionally adhering Mo to an iron-based powder;Ref. No. POl53453-PCT-ZZ (24/26) _25- a Cu powder; and a graphite powder, wherein the a11oy steel powder for powder meta11urgy has a chemicalcomposition containing Mo: 0.2 mass% to 1.5 mass%, Cu: 0.5 mass% to 4.0mass%, and C: 0.1 mass% to 1.0 mass%, with a balance being Fe andincidenta1 impurities, and the iron-based powder has a mean partic1e size of 30 um to 120 um,and the Cu powder is a mixed powder of a Cu powder having a mean partic1esize of 25 um or 1ess and a Cu powder having a f1at shape and satisfying are1ation L S -2d + 50 where d is a thickness of the Cu powder in um and L is diameter in a major axis of the Cu powder in um.
    [4] 4. A sintered body produced using the a11oy stee1 powder for powder meta11urgy according to any one of c1aims 1 to 3 as a materia1. Ref. No. PO153453-PCT-ZZ (25/26)
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    CA2992092C|2020-04-07|Mixed powder for powder metallurgy, sintered body, and method of manufacturing sintered body
    JP6819624B2|2021-01-27|Iron-based mixed powder for powder metallurgy, its manufacturing method, and sintered body with excellent tensile strength and impact resistance
    JP5929084B2|2016-06-01|Alloy steel powder for powder metallurgy, iron-based sintered material and method for producing the same
    WO2018143088A1|2018-08-09|Mixed powder for powder metallurgy, sintered body, and method for producing sintered body
    WO2018142778A1|2018-08-09|Mixed powder for powder metallurgy, sintered body, and method for producing sintered body
    同族专利:
    公开号 | 公开日
    JP2017226921A|2017-12-28|
    US20170259340A1|2017-09-14|
    KR20170080668A|2017-07-10|
    JP6394768B2|2018-09-26|
    CN107000052B|2019-10-25|
    US10207328B2|2019-02-19|
    SE542048C2|2020-02-18|
    CA2968321A1|2016-06-09|
    KR102014620B1|2019-08-26|
    JP2016108651A|2016-06-20|
    JP6222189B2|2017-11-01|
    CA2968321C|2020-06-02|
    CN107000052A|2017-08-01|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JPH04285141A|1991-03-14|1992-10-09|Kawasaki Steel Corp|Manufacture of ferrous sintered body|
    CA2069700C|1991-05-28|1998-08-18|Jinsuke Takata|Mixed powder for powder metallurgy and sintered product thereof|
    JPH05302101A|1991-05-28|1993-11-16|Kobe Steel Ltd|Mixed powder for powder metallurgy/and its sintered compact|
    JP3484674B2|1994-09-21|2004-01-06|同和鉄粉工業株式会社|Method for producing iron-based copper composite powder for powder metallurgy|
    JP3326072B2|1995-04-25|2002-09-17|川崎製鉄株式会社|Iron-based mixture for powder metallurgy and method for producing the same|
    JPH0931612A|1995-07-20|1997-02-04|Mitsubishi Materials Corp|Iron-base sintered alloy excellent in strength and wear resistance|
    JP3663929B2|1998-08-20|2005-06-22|Ｊｆｅスチール株式会社|Mixed powder for high strength sintered parts|
    JP4001450B2|2000-05-02|2007-10-31|日立粉末冶金株式会社|Valve seat for internal combustion engine and manufacturing method thereof|
    JP3651420B2|2000-08-31|2005-05-25|Ｊｆｅスチール株式会社|Alloy steel powder for powder metallurgy|
    JP4145127B2|2002-11-22|2008-09-03|三井金属鉱業株式会社|Flake copper powder, method for producing the flake copper powder, and conductive paste using the flake copper powder|
    JP4093070B2|2003-01-29|2008-05-28|Ｊｆｅスチール株式会社|Alloy steel powder|
    CN100515613C|2004-04-22|2009-07-22|杰富意钢铁株式会社|Mixed powder for powder metallurgy|
    JP4918966B2|2005-04-20|2012-04-18|株式会社ダイヤメット|Manufacturing method of sliding parts|
    JP4789837B2|2007-03-22|2011-10-12|トヨタ自動車株式会社|Iron-based sintered body and manufacturing method thereof|
    JP2009242887A|2008-03-31|2009-10-22|Jfe Steel Corp|Iron-based powdery mixture|
    US10081056B2|2011-09-22|2018-09-25|Ntn Corporation|Sintered bearing and method for manufacturing same|
    JP5972588B2|2012-02-02|2016-08-17|Ntn株式会社|Manufacturing method of sintered bearing|
    JP5565420B2|2012-02-02|2014-08-06|新日鐵住金株式会社|UOE steel pipe for line pipe|
    JP6244210B2|2013-03-04|2017-12-06|株式会社神戸製鋼所|Binder for powder metallurgy, mixed powder for powder metallurgy, and sintered body|
    JP6227903B2|2013-06-07|2017-11-08|Ｊｆｅスチール株式会社|Alloy steel powder for powder metallurgy and method for producing iron-based sintered body|
    JP5929967B2|2013-06-07|2016-06-08|Ｊｆｅスチール株式会社|Alloy steel powder for powder metallurgy|
    JP5741649B2|2013-08-20|2015-07-01|Ｊｆｅスチール株式会社|Iron-based powder mixture|
    US20160223016A1|2013-10-03|2016-08-04|Ntn Corporation|Sintered bearing and manufacturing process therefor|US20180193911A1|2015-09-11|2018-07-12|Jfe Steel Corporation|Method of producing mixed powder for powder metallurgy, method of producing sintered body, and sintered body|
    WO2017047101A1|2015-09-18|2017-03-23|Ｊｆｅスチール株式会社|Iron-based sintered compact and method for producing same|
    CN108025357B|2015-09-18|2020-03-03|杰富意钢铁株式会社|Mixed powder for powder metallurgy, sintered body, and method for producing sintered body|
    JP6627856B2|2017-02-02|2020-01-08|Ｊｆｅスチール株式会社|Method for producing powder mixture for powder metallurgy and sintered body|
    WO2018143088A1|2017-02-02|2018-08-09|Ｊｆｅスチール株式会社|Mixed powder for powder metallurgy, sintered body, and method for producing sintered body|
    WO2019087863A1|2017-10-30|2019-05-09|Ｔｐｒ株式会社|Iron-based sintered alloy valve guide and method for manufacturing same|
    WO2019111833A1|2017-12-05|2019-06-13|Ｊｆｅスチール株式会社|Steel alloy powder|
    CA3084618A1|2017-12-05|2019-06-13|Jfe Steel Corporation|Partially diffusion-alloyed steel powder|
    WO2019188833A1|2018-03-26|2019-10-03|Ｊｆｅスチール株式会社|Powder metallurgy alloy steel powder and powder metallurgy iron-based powder mixture|
    JP6930590B2|2018-03-26|2021-09-01|Ｊｆｅスチール株式会社|Alloy steel powder for powder metallurgy and iron-based mixed powder for powder metallurgy|
    KR102073269B1|2018-04-26|2020-02-05|지케이에스|Iron based powders for powder metallurgy and its manufacturing method|
    EP3950174A1|2019-04-05|2022-02-09|JFE Steel Corporation|Iron-based mixed powder for powder metallurgy, and iron-base sintered body|
    CN112063933A|2020-09-02|2020-12-11|苏州萨伯工业设计有限公司|Powder metallurgy formula for oil replenishing pump rotor|
    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    JP2014246946|2014-12-05|
    JP2015171401A|JP6222189B2|2014-12-05|2015-08-31|Alloy steel powder and sintered body for powder metallurgy|
    PCT/JP2015/005842|WO2016088333A1|2014-12-05|2015-11-24|Alloy steel powder for powder metallurgy, and sintered compact|
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