EP2666981A1 - Ventilsitz aus einer sinterlegierung auf eisenbasis - Google Patents

Ventilsitz aus einer sinterlegierung auf eisenbasis Download PDF

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Publication number
EP2666981A1
EP2666981A1 EP12736573.2A EP12736573A EP2666981A1 EP 2666981 A1 EP2666981 A1 EP 2666981A1 EP 12736573 A EP12736573 A EP 12736573A EP 2666981 A1 EP2666981 A1 EP 2666981A1
Authority
EP
European Patent Office
Prior art keywords
valve seat
hard particles
iron
matrix
based sintered
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Withdrawn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
EP12736573.2A
Other languages
English (en)
French (fr)
Other versions
EP2666981A4 (de
Inventor
Rintarou Takahashi
Hiroji Henmi
Syuuichi SHIKANAI
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.)
Riken Corp
Original Assignee
Riken Corp
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Filing date
Publication date
Application filed by Riken Corp filed Critical Riken Corp
Publication of EP2666981A1 publication Critical patent/EP2666981A1/de
Publication of EP2666981A4 publication Critical patent/EP2666981A4/de
Withdrawn legal-status Critical Current

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Classifications

    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
    • F01L3/02—Selecting particular materials for valve-members or valve-seats; Valve-members or valve-seats composed of two or more materials
    • 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
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F5/008—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of engine cylinder parts or of piston parts other than piston rings
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/04—Alloys based on tungsten or molybdenum
    • 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
    • C22C33/0207—Using a mixture of prealloyed powders or a master alloy
    • C22C33/0221—Using a mixture of prealloyed powders or a master alloy comprising S or a sulfur compound
    • 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
    • C22C33/0228—Using a mixture of prealloyed powders or a master alloy comprising other non-metallic compounds or more than 5% of graphite
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L1/00—Valve-gear or valve arrangements, e.g. lift-valve gear
    • F01L1/02—Valve drive
    • F01L1/04—Valve drive by means of cams, camshafts, cam discs, eccentrics or the like
    • F01L1/047—Camshafts
    • F01L1/053—Camshafts overhead type
    • F01L1/0532—Camshafts overhead type the cams being directly in contact with the driven valve
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L1/00—Valve-gear or valve arrangements, e.g. lift-valve gear
    • F01L1/12—Transmitting gear between valve drive and valve
    • F01L1/14—Tappets; Push rods
    • F01L1/143—Tappets; Push rods for use with overhead camshafts
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2303/00—Manufacturing of components used in valve arrangements
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2800/00—Methods of operation using a variable valve timing mechanism
    • F01L2800/18—Testing or simulation
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2810/00—Arrangements solving specific problems in relation with valve gears
    • F01L2810/02—Lubrication
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2820/00—Details on specific features characterising valve gear arrangements
    • F01L2820/01—Absolute values

Definitions

  • the present invention relates to a valve seat for internal combustion engines, particularly to a valve seat made of an iron-based sintered alloy, which is used under the condition of low lubrication by fuel injection into cylinders.
  • valve seats used with intake valves and exhaust valves for keeping the gas tightness of combustion chambers are exposed to combustion pressure, and receive strong shock repeatedly by the reciprocating motion of valves.
  • valves are not only reciprocatable but also rotatable around their stems, sliding surfaces of valve seats which come into contact with valves are required to have high wear resistance.
  • DI direct injection
  • iron-based sintered alloys having high wear resistance under no lubrication which is improved by dispersing a large amount of solid lubricants such as calcium fluoride, etc. in the matrix to increase self-lubrication, as described in JP 2003-166025 A , have been used for valve seats.
  • valve seats of conventional iron-based sintered alloys in which calcium fluoride as a solid lubricant is dispersed in a large amount in a matrix, have low strength, as well as insufficient wear resistance in a low temperature range, so that they are not suitable for use in a wide temperature range.
  • valve seats of conventional iron-based sintered alloys containing only ferromolybdenum as hard particles have insufficient wear resistance in a wide temperature range.
  • an object of the present invention is to provide a valve seat of an iron-based sintered alloy having high wear resistance in a wide temperature range, which can be used in direct injection engines with improved fuel efficiency, low emission and high power.
  • the inventors have found that by limiting the amount of a solid lubricant dispersed in the matrix of the valve seat of an iron-based sintered alloy, and dispersing at least two types of hard particles having different hardnesses in the matrix, the valve seat can be provided with high strength and self-lubrication, as well as remarkably improved wear resistance under no lubrication in a wide temperature range.
  • the present invention provides a valve seat of an iron-based sintered alloy, in which at least two types of hard particles having different hardnesses, and 0.2-0.8% by mass of a solid lubricant are dispersed.
  • At least two types of the hard particles having different hardnesses preferably comprise 2-8% by mass of first hard particles having an average particle size of 50-150 ⁇ m and Vickers hardness Hv of 800-1200, and 5-15% by mass of second hard particles having an average particle size of 10-150 ⁇ m and Vickers hardness Hv of 400-750.
  • the hard particles may be Fe-Mo alloy particles, Fe-Cr-Mo-V alloy particles, and Co-Mo-Cr alloy particles.
  • the first hard particles are Fe-Mo-Si alloy particles comprising by mass 40-70% of Mo, and 0.1-2.0% of Si, the balance being Fe and inevitable impurities
  • the second hard particles are Fe-C-Cr-Mo-V alloy particles comprising by mass 0.2-0.5% of C, 0.5-5% of Cr, 1-5% of Mo, and 2-5% of V, the balance being Fe and inevitable impurities.
  • the matrix in which at least two types of the hard particles having different hardnesses and the solid lubricant are dispersed, preferably has a composition comprising by mass 0.5-2.5% of C, 0.4-2% of Si, 0.5-5% of Mo, and 1-5% of Ni, the balance being Fe and inevitable impurities.
  • the matrix phase preferably has a tempered martensite phase and a pearlite phase.
  • the solid lubricant is preferably constituted by one or more powders selected from the group consisting of sulfides such as MnS and MoS 2 and nitrides such as BN, having an average particle size of 2-50 ⁇ m.
  • Fig. 1 is a view schematically showing a wear rig test for evaluating the valve seat of an iron-based sintered alloy according to the present invention.
  • Fig. 2(a) is a graph showing by a relative value the amounts of wear of a valve seat and a valve at a test temperature of 150°C, which was measured on each of the valve seats of Examples within the present invention and Comparative Examples by a wear rig tester.
  • Fig. 2(b) is a graph showing by a relative value the amounts of wear of a valve seat and a valve at a test temperature of 250°C, which was measured on each of the valve seats of Examples within the present invention and Comparative Examples by a wear rig tester.
  • Fig. 3 (a) is a graph showing by a relative value the total amount of wear of a valve seat and a valve at a test temperature of 150°C, which was measured on each of the valve seats of Examples within the present invention and Comparative Examples by a wear rig tester.
  • Fig. 3(b) is a graph showing by a relative value the total amount of wear of a valve seat and a valve at a test temperature of 250°C, which was measured on each of the valve seats of Examples within the present invention and Comparative Examples by a wear rig tester.
  • the valve seat of an iron-based sintered alloy according to the present invention is composed of a matrix, at least two types of hard particles having different hardnesses and a solid lubricant, which are disperseddisposed in the matrix.
  • the solid lubricant dispersed in the matrix is 0.2-0.8% by mass. More than 0.8% of the solid lubricant dispersed reduces powder-bonding strength in powder compression molding, resulting in a sintered body with low strength and insufficient wear resistance. On the other hand, less than 0.2% of the solid lubricant provides low machinability.
  • the solid lubricant preferably has an average particle size of 2-50 ⁇ m. The solid lubricant uniformly dispersed in the matrix improves wear resistance, self-lubrication and machinability.
  • the solid lubricant is preferably one or more selected from sulfides such as MnS, MoS 2 , etc., and nitrides such as BN (boron nitride), etc. It is more preferable that when two or more types of solid lubricants are used, at least one has an average particle size of 2-10 ⁇ m, and the other has an average particle size of 10-50 ⁇ m, for uniform dispersion.
  • the fine dispersion of the solid lubricant having an average particle size of 2-10 ⁇ m improves the machinability, and the coarse dispersion of the solid lubricant having a particle size range of 10-50 ⁇ m improves the self-lubrication and the wear resistance.
  • first hard particles are harder than second hard particles, which are harder than the matrix phase.
  • the presence of hard particles having intermediate hardness can provide the matrix phase and the hard particles with good hardness balance, thereby suppressing attackability to a matemating member while maintaining the wear resistance.
  • the first hard particles dispersed in an amount of 2-8% by mass preferably have an average particle size of 50-150 ⁇ m and Vickers hardness Hv of 800-1200. It is particularly preferable to use particles of an Fe-Mo-Si alloy, an intermetallic compound comprising by mass 40-70% of Mo, and 0.1-2.0% of Si, the balance being Fe and inevitable impurities. Used with the second hard particles described later, they can suppress the diffusion of alloying elements into the matrix, increasing softening resistance without modifying the matrix structure, thereby suppressing attackability to a matemating member and improving the wear resistance of itself.
  • the second hard particles dispersed in an amount of 5-15% by mass preferably have an average particle size of 10-150 ⁇ m and Vickers hardness Hv of 400-750, harder than the matrix. Their average particle size is more preferably 20-130 ⁇ m. It is particularly preferable to use particles of an Fe-C-Cr-Mo-V alloy comprising by mass 0.2-0.5% of C, 0.5-5% of Cr, 1-5% of Mo, and 2-5% of V, the balance being Fe and inevitable impurities.
  • part of alloying elements for example, Cr and V
  • the matrix preferably has a composition comprising by mass 0.5-2.5% of C, 0.4-2% of Si, 0.5-5% of Mo, and 1-5% of Ni, the balance being Fe and inevitable impurities.
  • C is dissolved in the matrix to strengthen it, and combined with other alloying elements to form carbides, improving the wear resistance.
  • Si forms an oxide layer to improve the wear resistance.
  • Mo improves the hardenability, strengthens the matrix, and lowers the oxidation start temperature of the valve seat, thereby providing the valve seat with improved wear resistance.
  • Ni strengthens the matrix and improves the hardness, thereby improving the wear resistance.
  • the matrix preferably has a mixed structure comprising tempered martensite and pearlite, so that it has proper toughness and excellent wear resistance. Of course, fine carbides are dispersed in the mixed structure.
  • a starting material for the matrix phase may be iron powder mixed with alloying element powders, graphite powder, etc., or prealloy powder having a predetermined composition.
  • Iron powder and/or prealloy powder and alloying element powders constituting the matrix phase are mixed with at least two types of hard particles having different hardnesses and solid lubricant powder, to prepare a starting material powder.
  • 0.5-2% of stearate, etc. may be added as a parting agent to the total amount of the powder mixture, a starting material powder comprising iron powder, prealloy powder, alloying element powders, hard particles, and solid lubricant powder.
  • the powder mixture is compression-molded to a green compact by a press, etc., and the green compact is sintered in a temperature range of 1050-1200°C in vacuum or in a non-oxidizing (or reducing) atmosphere, and then tempered in a temperature range of 500-700°C.
  • the sintered body after tempering may be sealed by a resin, etc.
  • the sintering temperature of lower than 1050°C provides insufficient diffusion bonding, failing to obtain the desired strength.
  • the non-oxidizing (or reducing) atmosphere is preferably an NH 3 gas, a mixed gas of N 2 and H 2 , etc.
  • Pure iron powder, and/or prealloy powder comprising 2.5% of Mo, 1% of Si, and 0.02% of C, the balance being iron and inevitable impurities, each of which had a particle size distribution with a peak in 150-200 mesh, were mixed with Mo powder, Si powder, Ni powder and graphite powder in such amounts as to provide the composition of Matrix A-K shown in Table 1, and with the first hard particles L-R of Fe-Mo-Si alloys shown in Table 2, the second hard particles S-Y of Fe-C-Cr-Mo-V alloys shown in Table 3, and the solid lubricant powder shown in Table 4, at ratios (% by mass) shown in Table 4, and blended by a blender to prepare each powder mixture.
  • Each powder mixture was charged into a molding die, compression-molded by a press at pressure of 6.5 t/cm 2 , and then sintered at 1120°C in vacuum to produce a ring-shaped sintered body of 37.6 mm in outer diameter, 26 mm in inner diameter and 8 mm in thickness.
  • Comparative Examples using each powder mixture of Comparative Examples 1(C1), 2 (C2) and 4-6 (C4-C6), in which the total amount of solid lubricants was 1% or more, and Comparative Examples 3 and 4 (C3 and C4), in which one type of hard particles were contained, a ring-shaped sintered body of Comparative Examples 1-6 (C1-C6) was produced by the same steps as in Examples 1-5. In each sintered body, the matrix and hard particles were measured with respect to Vickers hardness at a load of 50-100 g by a micro Vickers hardness meter. The results are shown in Table 4.
  • Each ring-shaped sintered body was machined to a valve seat, whose wear resistance was evaluated by a wear rig tester shown in Fig. 1 .
  • the valve seat 4 was fit into a valve seat holder 2 made of the same material as for a cylinder head in the tester, to conduct a wear test by vertically reciprocating a valve 3 by the rotation of a cam 7, with the valve 3 and the valve seat 4 heated by a burner 1.
  • thermocouples 5, 6 embedded in the valve seat 4 the power of the burner 1 was controlled such that a contact surface of the valve seat was kept at a predetermined temperature.
  • valve seat 4 was worn, and their amounts of wear were expressed by the degrees of recession of the contact surfaces of the valve seat and the valve, which were calculated from their sizes measured before and after the test.
  • the valve used had a size corresponding to the valve seat, and was made of an SUH alloy (JIS G 4311).
  • the test conditions were as follows: Temperatures 150°C and 250°C, Rotation speed of cam 2500 rpm, and Test time 5 hours. The test results are shown in Table 5, Fig. 2(a) (at a test temperature of 150°C), and Fig. 2(b) (at a test temperature of 250°C).
  • each valve seat is expressed by a relative value, assuming that the amount of wear is 1 in Comparative Example 3 (C3), in which only hard particles of an Fe-Mo-Si alloy were dispersed.
  • Any valve seats and their matemating members (valves) in Examples 1-5 (E1-E5) within the present invention were smaller in the amount of wear than in Comparative Example 3 (C3) at test temperatures of 150°C and 250°C, indicating that they had excellent wear resistance and relatively mild attackability to matemating members in both low and high temperature ranges.
  • the total amount of wear of the valve seat and the valve in Examples 1-5 (E1-E5) within the present invention was half or less that in Comparative Example 3 at 150°C and 250°C, indicating that they had remarkably improved wear resistance in a wide range from low temperatures to high temperatures.
  • Examples within the present invention were smaller in the amounts of wear of the valve seat and the matemating member than Comparative Examples in a wide range from low temperatures to high temperatures, indicating improved wear resistance and lower attackability to matemating members.
  • the valve seat of an iron-based sintered alloy according to the present invention which comprises 0.2-0.8% by mass of a solid lubricant and at least two types of hard particles having different hardnesses dispersed in the matrix, has high strength as well as self-lubrication, thereby exhibiting extremely improved wear resistance under no lubrication in a wide temperature range.
  • Two types of hard particles contribute to improving wear resistance at high and low temperatures, because part of elements constituting one type of hard particles are dissolved in the matrix or form compounds with elements in the matrix to strengthen the matrix, while suppressing elements constituting the other type of hard particles from being dissolved in the matrix, thereby increasing softening resistance.
  • valve seat used in DI-type engines in which fuel is directly injected into cylinders exhibits excellent wear resistance, under little lubrication and in a wide range from low temperatures of about 150-350°C to high temperatures.
  • the valve seat of an iron-based sintered alloy according to the present invention is more preferable as an intake valve seat.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)
EP12736573.2A 2011-01-20 2012-01-20 Ventilsitz aus einer sinterlegierung auf eisenbasis Withdrawn EP2666981A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2011009719A JP5823697B2 (ja) 2011-01-20 2011-01-20 鉄基焼結合金製バルブシート
PCT/JP2012/051191 WO2012099239A1 (ja) 2011-01-20 2012-01-20 鉄基焼結合金製バルブシート

Publications (2)

Publication Number Publication Date
EP2666981A1 true EP2666981A1 (de) 2013-11-27
EP2666981A4 EP2666981A4 (de) 2015-04-01

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP12736573.2A Withdrawn EP2666981A4 (de) 2011-01-20 2012-01-20 Ventilsitz aus einer sinterlegierung auf eisenbasis

Country Status (6)

Country Link
US (1) US20130291822A1 (de)
EP (1) EP2666981A4 (de)
JP (1) JP5823697B2 (de)
CN (1) CN103328776A (de)
MX (1) MX2013008435A (de)
WO (1) WO2012099239A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2927333A1 (de) * 2014-03-31 2015-10-07 Nippon Piston Ring Co., Ltd. Sinterlegierungsmaterial auf eisenbasis für ventilsitzeinsätze und verfahren zur herstellung davon

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Publication number Priority date Publication date Assignee Title
JP6427442B2 (ja) * 2015-03-09 2018-11-21 山陽特殊製鋼株式会社 Ｆｅ基焼結用硬質粉末およびそれを用いた耐摩耗性の優れたＦｅ基焼結体
JP6392796B2 (ja) * 2016-01-25 2018-09-19 トヨタ自動車株式会社 耐摩耗性鉄基焼結合金の製造方法、焼結合金用成形体、および耐摩耗性鉄基焼結合金
JP6352959B2 (ja) * 2016-02-04 2018-07-04 トヨタ自動車株式会社 耐摩耗性鉄基焼結合金の製造方法、焼結合金用成形体、および耐摩耗性鉄基焼結合金
EP3406865B1 (de) * 2017-03-28 2020-01-29 Kabushiki Kaisha Riken Gesinterter ventilsitz
JP6842345B2 (ja) * 2017-04-04 2021-03-17 トヨタ自動車株式会社 耐摩耗性鉄基焼結合金の製造方法
DE102018209682A1 (de) * 2018-06-15 2019-12-19 Mahle International Gmbh Verfahren zum Herstellen eines pulvermetallurgischen Erzeugnisses

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Publication number Priority date Publication date Assignee Title
JP2002129296A (ja) * 2000-10-27 2002-05-09 Nippon Piston Ring Co Ltd バルブシート用鉄基焼結合金材および鉄基焼結合金製バルブシート
JP2003166025A (ja) * 2001-11-29 2003-06-13 Riken Corp 硬質粒子分散型焼結合金及びその製造方法
EP1347067A1 (de) * 2002-03-12 2003-09-24 Kabushiki Kaisha Riken Sinterlegierung auf Eisenbasis zur Verwendung als Ventilsitz sowie Verfahren zu ihrer Herstellung
US20050193861A1 (en) * 2004-03-03 2005-09-08 Nippon Piston Ring Co., Ltd. Iron-based sintered alloy material for valve seat
US6951579B2 (en) * 2002-03-15 2005-10-04 Teikoku Piston Ring Co., Ltd. Sintered alloy for valve seats, valve seat and manufacturing method thereof
JP2006299404A (ja) * 2005-03-23 2006-11-02 Nippon Piston Ring Co Ltd 内燃機関用鉄基焼結合金製バルブシート材

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JPH0593241A (ja) * 1991-09-30 1993-04-16 Riken Corp バルブシート用鉄基焼結合金の製造方法
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WO2012099239A1 (ja) 2012-07-26
EP2666981A4 (de) 2015-04-01
JP2012149584A (ja) 2012-08-09

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