EP3026141A1 - Ventilführung aus sinterlegierung und verfahren zur herstellung davon - Google Patents

Ventilführung aus sinterlegierung und verfahren zur herstellung davon Download PDF

Info

Publication number
EP3026141A1
EP3026141A1 EP14829838.3A EP14829838A EP3026141A1 EP 3026141 A1 EP3026141 A1 EP 3026141A1 EP 14829838 A EP14829838 A EP 14829838A EP 3026141 A1 EP3026141 A1 EP 3026141A1
Authority
EP
European Patent Office
Prior art keywords
alloy
valve guide
phase
mass
based alloy
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Withdrawn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
EP14829838.3A
Other languages
English (en)
French (fr)
Other versions
EP3026141A4 (de
Inventor
Rintarou Takahashi
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
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 Riken Corp filed Critical Riken Corp
Publication of EP3026141A1 publication Critical patent/EP3026141A1/de
Publication of EP3026141A4 publication Critical patent/EP3026141A4/de
Withdrawn legal-status Critical Current

Links

Images

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
    • F01L3/08—Valves guides; Sealing of valve stem, e.g. sealing by lubricant
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
    • 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
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated 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
    • 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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0425—Copper-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
    • 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
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/06—Cast-iron alloys containing chromium
    • 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
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • 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
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/17—Metallic particles coated with metal
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/10—Copper
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/35—Iron

Definitions

  • the present invention relates to a valve guide for guiding the opening and closing of an engine valve, and its production method, particularly to a high-thermal-conductivity valve guide capable of suppressing valve temperature elevation, and its production method.
  • JP 6-306554 discloses a sintered alloy valve guide having a pearlite-based matrix having a composition comprising by weight 1-4% of C, 1.5-6% of Cu, and 0.1-0.8% of P, the balance being Fe and inevitable impurities, in which Fe-C-P compounds and free graphite are dispersed.
  • Valve guides having high valve-cooling capability are made of, for example, brass, but they suffer poor material properties such as insufficient wear resistance, etc., and cost disadvantages such as higher machining cost than conventional iron-based valve guides, etc. Accordingly, sintered alloy valve guides having high valve-cooling capability and wear resistance while meeting cost requirements are desired.
  • JP 11-323512 A discloses a sintered iron-based alloy valve guide produced by mixing, molding and sintering Fe powder, C powder and Cu-Ni alloy powder, which has a structure in which fine precipitates of a free graphite phase having an average particle size of 30 ⁇ m or less are dispersed in a matrix of an Fe-based alloy phase bound by a Cu-based alloy phase, the Fe-based alloy phase having a composition comprising by weight 20-40% of Cu, 0.6-14% of Ni, and 1.0-3.0% of C, the balance being Fe and inevitable impurities.
  • an object of the present invention is to provide a sintered alloy valve guide having high thermal conductivity and excellent wear resistance, which can be used in engines subjected to a large thermal load due to downsizing, direct injection and supercharging, and a method for producing such a sintered alloy valve guide.
  • the sintered alloy valve guide of the present invention has a composition comprising by mass 10-90% of Cu, 0-10% of Cr, 0-6% of Mo, 0-8% of V, 0-8% of W, and 0.5-3% of C, the balance being substantially Fe and inevitable impurities, the total amount of Cr, Mo, V and W being 2% or more, and a structure comprising an Fe-based alloy phase, a Cu or Cu-based alloy phase, and a graphite phase.
  • the Fe-based alloy phase is preferably an Fe-Mo-C alloy, an Fe-Cr-Mo-V-C alloy, an Fe-Cr-V-W-C alloy, or an Fe-Cr-Mo-V-W-C alloy. It preferably has a composition comprising by mass 0-10% of Cr, 0-6% of Mo, 0-8% of V, 0-8% of W, and 0.5-1% of C, the balance being substantially Fe and inevitable impurities, the total amount of Cr, Mo, V and W being 2% or more.
  • the Cu or Cu-based alloy phase is preferably continuous in the structure.
  • the Cu or Cu-based alloy phase preferably has thermal conductivity of 200 W/mK or more.
  • the sintered alloy valve guide of the present invention is produced by coating prealloy powder having a composition comprising by mass 0-10% of Cr, 0-6% of Mo, 0-8% of V, 0-8% of W, and 0.5-1 % of C, the balance being substantially Fe and inevitable impurities, the total amount of Cr, Mo, V and W being 2% or more, with Cu, mixing the Cu-coated prealloy powder with C powder, and then molding and sintering.
  • the sintered alloy valve guide of the present invention has a composition comprising by mass 10-90% of copper (Cu), 0-10% of chromium (Cr), 0-6% of molybdenum (Mo), 0-8% of vanadium (V), 0-8% of tungsten (W), and 0.5-3% of carbon (C), the balance being iron (Fe) and inevitable impurities, the total amount of Cr, Mo, V and W being 2% or more.
  • the sintered alloy valve guide of the present invention also has a structure comprising an Fe-based alloy phase, a Cu or Cu-based alloy phase, and a graphite phase contributing to wear resistance, thermal conductivity, and self-lubrication.
  • the Fe-based alloy phase comprises Fe as a main component
  • the Cu-based alloy phase comprises Cu as a main component.
  • Cu is an indispensable alloy component to have high thermal conductivity.
  • the thermal conductivity of the sintered alloy valve guide is preferably 30 W/(m•K) or more, more preferably 50 W/mK or more.
  • Less than 10% by mass of Cu generates an insufficient liquid phase, as well as an insufficient Cu or Cu-based alloy phase, failing to obtain a dense sintered alloy having desired thermal conductivity.
  • more than 90% by mass of Cu forms too small an amount of the Fe-based alloy phase, resulting in poor wear resistance.
  • Cu is 10-90% by mass.
  • Cu is preferably 30% or more by mass and 80% or less by mass, more preferably 75% or less by mass.
  • the Cu-based alloy phase in the present invention may be a Cu-Cr alloy, a Cu-Fe alloy or a Cu-Cr-Fe alloy. Each of these Cu-based alloy phases can have thermal conductivity of 200 W/mK or more.
  • Ni is not contained in the present invention, because Ni forms a solid solution with Cu at any ratio, undesirably extremely reducing the thermal conductivity.
  • Cr, Mo, V and W are dissolved in the Fe-based alloy phase, contributing to improvement in strength and hardness. They further form carbides to improve wear resistance. When the total amount of Cr, Mo, V and W is less than 2.0% by mass, good heat resistance and wear resistance cannot be obtained. On the other hand, when Cr exceeds 10% by mass, when Mo exceeds 6% by mass, or when each of V and W exceeds 8% by mass, excessive or coarse precipitates are formed, weakening the Fe-based alloy phase, increasing the attacking of a mating member, or suffering breakage when pressed into a cylinder head.
  • the amounts of Cr, Mo, V and W added are by mass 0-10% of Cr, 0-6% of Mo, 0-8% of V, and 0-8% of W, the total amount of Cr, Mo, V and W being 2% or more.
  • the upper limit of the total amount of Cr, Mo, V and W is 32% by mass, but it is preferably 16% or less by mass taking into consideration the attacking of a mating member.
  • C is dissolved in the Fe-based alloy phase or forms carbides, to improve the strength and hardness of the alloy. It is also dispersed as graphite, imparting self-lubrication to the alloy.
  • C is less than 0.5% by mass, sufficient carbides are not precipitated, failing to obtain the above effects.
  • C exceeds 3% by mass, excessive carbides or too coarse carbides are precipitated, resulting in reduced toughness, and thus lower performance. Accordingly, C is 0.5-3% by mass.
  • Fe-based alloy powder having a composition comprising by mass 0-10% of Cr, 0-6% of Mo, 0-8% of V, 0-8% of W, and 0.5-1% of C, the balance being substantially Fe and inevitable impurities, the total amount of Cr, Mo, V and W being 2% or more, is used as a starting material powder.
  • a Cu component may be added by mixing the Fe-based alloy powder with a Cu or Cu-based alloy powder, or by coating the Fe-based alloy powder with Cu.
  • a Cu coating may be formed by plating the Fe-based alloy powder with Cu, the mechanical alloying of the Fe-based alloy powder with Cu powder, etc., and Cu plating is preferable.
  • the Fe-based alloy powder is preferably formed by water atomization, and subjected to immersion plating in an electroless plating solution to form a predetermined Cu component layer.
  • the C powder is preferably graphite powder having an average particle size of 1-20 ⁇ m.
  • the starting material powder may contain stearate, etc. as a parting agent.
  • the above starting material powders are mixed, and the resultant mixed powder is charged into a die, compression-molded by pressing, etc., degreased, if necessary, and then sintered at 900-1050°C in vacuum.
  • the sintering temperature of lower than 900°C fails to obtain a sintered body having a desired structure because of an insufficient liquid phase formed from Cu or its alloy, and the sintering temperature of higher than 1050°C cannot keep a predetermined shape of the sintered body because of too much a liquid phase formed from Cu or its alloy.
  • the sintering temperature is 900-1050°C.
  • Fe-based prealloy powder having a composition comprising by mass 1.33% of Cr, 2.67% of Mo, 4.00% of V and 0.57% of C was electroless-plated with Cu, to form Cu-coated powder (Cu: 45.5% by mass per 100% by mass of the entire powder), and mixed with graphite powder to form mixed powder (C: about 2% per 100% of the entire mixture). 0.5% by mass of zinc stearate was added to and blended with 100% by mass of the mixed powder to form a starting material powder mixture.
  • This starting material powder mixture was charged into a die, and compression-molded by pressing at pressure of 6.5 t/cm 2 to form a green body, which was degreased, and then sintered at 1000°C in vacuum to produce a cylindrical sintered body of 15 mm in diameter and 50 mm in height.
  • Fig. 1 is an optical photomicrograph showing the structure of the sintered body of Example 1.
  • the sintered body had a relatively dense structure comprising relatively coarse Fe-based alloy phase particles 1, a Cu (or Cu-based alloy) phase 2, and relatively fine graphite phase particles 3, with pores 4 slightly observed. It is characterized by a continuous Cu (or Cu-based alloy) phase 2.
  • valve guide test piece of 10 mm x 50 mm x 10 mm was machined from the cylindrical sintered body, and a valve test piece (sliding mating member) of 8 mm in diameter and 30 mm in length, whose one end had an 8-mm-R cylindrical surface, was cut out of an SUH alloy valve material. As shown in Fig. 2 , the valve test piece 6 was pushed to the reciprocally moving valve guide test piece 5 under a constant load to evaluate wear resistance.
  • the test conditions were as follows.
  • Example 1 The receding amounts of contact surfaces of the valve guide test piece and the valve test piece after the test were regarded as wear. As a result, the wear in Example 1 was 2.0 ⁇ m in the valve guide test piece, and 21.5 ⁇ m in the valve test piece.
  • a disc-shaped test piece of 5.0 mm in diameter and 1.0 mm in thickness was cut out of the cylindrical sintered body, mirror-polished on bottom surfaces, and its thermal conductivity was measured by a laser flash method.
  • the thermal conductivity in Example 1 was 50 W/mK.
  • Sintered bodies were produced in the same manner as in Example 1, except for changing the Fe-based prealloy composition, the amount of electroless Cu plating, and the amount of C powder added as shown in the column of "Chemical Components" in Table 1.
  • a valve guide test piece for the wear test and a disc-shaped test piece for the thermal conductivity measurement were formed from each sintered body, and subjected to the same wear test and thermal conductivity measurement as in Example 1. The results are shown in Table 1 together with those of Example 1.
  • Comparative Examples 1 and 2 in which the total amount of alloy elements is less than 2% by mass, the valves (sliding mates) suffer little wear, but the valve guides per se suffer increased wear. Particularly in Comparative Example 2 containing a small total amount of the alloy elements and more than 90% by mass of the Cu component, the valve guide per se suffers drastically increased wear because of insufficient strength and hardness. Because in Comparative Examples 3-5, any of the alloy elements (all of Cr, Mo, V and W in Comparative Example 3, W in Comparative Example 4, and Cr in Comparative Example 5) is more than the required amount, the valves (mating members) suffer large wear, though the valve guides undergo little wear. Further, they have as insufficiently low thermal conductivity as 20 W/mK or less.
  • the sintered alloy valve guide of the present invention comprises a wear-resistant Fe-based alloy phase, a Cu or Cu-based alloy phase having excellent thermal conductivity, and a graphite phase having excellent self-lubrication, it has excellent wear resistance and high valve-cooling capability, thereby avoiding abnormal combustion such as knocking, etc. in high-performance, high-load engines, and contributing to improving engine performance.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • General Engineering & Computer Science (AREA)
  • Powder Metallurgy (AREA)
EP14829838.3A 2013-07-26 2014-07-22 Ventilführung aus sinterlegierung und verfahren zur herstellung davon Withdrawn EP3026141A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2013155336A JP5658804B1 (ja) 2013-07-26 2013-07-26 焼結合金製バルブガイド及びその製造方法
PCT/JP2014/069284 WO2015012249A1 (ja) 2013-07-26 2014-07-22 焼結合金製バルブガイド及びその製造方法

Publications (2)

Publication Number Publication Date
EP3026141A1 true EP3026141A1 (de) 2016-06-01
EP3026141A4 EP3026141A4 (de) 2017-03-29

Family

ID=52393284

Family Applications (1)

Application Number Title Priority Date Filing Date
EP14829838.3A Withdrawn EP3026141A4 (de) 2013-07-26 2014-07-22 Ventilführung aus sinterlegierung und verfahren zur herstellung davon

Country Status (5)

Country Link
US (1) US20160160700A1 (de)
EP (1) EP3026141A4 (de)
JP (1) JP5658804B1 (de)
CN (1) CN105452507B (de)
WO (1) WO2015012249A1 (de)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6507848B2 (ja) * 2015-05-25 2019-05-08 住友金属鉱山株式会社 スパッタリング用合金ターゲット、及びスパッタリング用合金ターゲットの製造方法
DE102015109621A1 (de) * 2015-06-16 2016-12-22 Bleistahl-Produktions Gmbh & Co Kg. Ventilführung
CN105463291B (zh) * 2015-12-09 2017-03-22 博深工具股份有限公司 全预合金化粉末及其制备方法
JP6514421B1 (ja) * 2017-10-30 2019-05-15 Ｔｐｒ株式会社 鉄基焼結合金製バルブガイドおよびその製造方法
US20200216935A1 (en) * 2019-01-04 2020-07-09 Tenneco Inc. Hard powder particles with improved compressibility and green strength
DE102020213651A1 (de) * 2020-10-29 2022-05-05 Mahle International Gmbh Verschleißfeste, hochwärmeleitfähige Sinterlegierung, insbesondere für Lageranwendungen und Ventilsitzringe

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001295004A (ja) * 2000-02-09 2001-10-26 Mitsubishi Materials Corp 鉄基焼結合金
JP2003027183A (ja) * 2002-06-12 2003-01-29 Mitsubishi Materials Corp 鉄基焼結合金製シンクロナイザーリング
US20120177528A1 (en) * 2005-01-31 2012-07-12 Takemori Takayama Sintered material, ferrous sintered sliding material, producing method of the same, sliding member, producing method of the same and coupling device

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5739104A (en) * 1980-08-20 1982-03-04 Mitsubishi Metal Corp Production of valve seat made of fe based sintered alloy
JPS58157951A (ja) * 1982-03-12 1983-09-20 Hitachi Powdered Metals Co Ltd 摺動部材用焼結合金
JP2812137B2 (ja) 1993-04-22 1998-10-22 三菱マテリアル株式会社 耐摩耗性のすぐれたＦｅ基焼結合金製バルブガイド部材
JPH11323512A (ja) 1998-05-12 1999-11-26 Mitsubishi Materials Corp 鉄基焼結合金製バルブガイドおよびその製造方法
US8257462B2 (en) * 2009-10-15 2012-09-04 Federal-Mogul Corporation Iron-based sintered powder metal for wear resistant applications
JP5649830B2 (ja) * 2010-02-23 2015-01-07 株式会社リケン バルブシート

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001295004A (ja) * 2000-02-09 2001-10-26 Mitsubishi Materials Corp 鉄基焼結合金
JP2003027183A (ja) * 2002-06-12 2003-01-29 Mitsubishi Materials Corp 鉄基焼結合金製シンクロナイザーリング
US20120177528A1 (en) * 2005-01-31 2012-07-12 Takemori Takayama Sintered material, ferrous sintered sliding material, producing method of the same, sliding member, producing method of the same and coupling device

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of WO2015012249A1 *

Also Published As

Publication number Publication date
JP2015025169A (ja) 2015-02-05
EP3026141A4 (de) 2017-03-29
US20160160700A1 (en) 2016-06-09
CN105452507A (zh) 2016-03-30
WO2015012249A1 (ja) 2015-01-29
CN105452507B (zh) 2018-11-06
JP5658804B1 (ja) 2015-01-28

Similar Documents

Publication Publication Date Title
EP3026141A1 (de) Ventilführung aus sinterlegierung und verfahren zur herstellung davon
JP4891421B2 (ja) 粉末冶金用混合物及びこれを用いた粉末冶金部品の製造方法
US6951579B2 (en) Sintered alloy for valve seats, valve seat and manufacturing method thereof
JP6577173B2 (ja) Ｃｕ基焼結合金及びその製造方法
CN101576118B (zh) 无铅铜基滑动轴承材料及其制备方法
EP3162475B1 (de) Gesinterter ventilsitz und verfahren zur herstellung davon
US20090311129A1 (en) Abrasion resistant sintered copper base cu-ni-sn alloy and bearing made from the same
CN102762755B (zh) 阀座
CN101871058A (zh) 一种金属基自润滑复合材料及其制备方法
WO2015141331A1 (ja) 鉄基焼結合金製バルブシート
JP2005248234A (ja) バルブシート用鉄基焼結合金材
EP2666981A1 (de) Ventilsitz aus einer sinterlegierung auf eisenbasis
WO2018179590A1 (ja) 焼結バルブシート
JPWO2017057464A1 (ja) 焼結バルブシート
EP2511388B1 (de) Gesintertes gleitelement
EP3296418A1 (de) Herstellungsverfahren für verschleissfeste gesinterte legierung auf eisenbasis sowie verschleissfeste gesinterte legierung auf eisenbasis
WO2010147139A1 (ja) 焼結摺動材料及びその製造方法
CN1018657B (zh) 耐热耐磨自润滑材料及其制造方法
US20200284173A1 (en) Sintered ferrous alloy valve seat exhibiting excellent thermal conductivity for use in internal combustion engine
KR101717347B1 (ko) 내마모성 구리계 소결 합금
EP2562279A1 (de) Kupferlegierung für ein gleitelement
JP2021139365A (ja) バルブガイド
EP3636369A1 (de) Sinterlegierung auf eisenbasis und herstellungsverfahren dafür
JPS61291954A (ja) 高温耐摩耐食焼結材料及びその製造方法
JP3942136B2 (ja) 鉄基焼結合金

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20160128

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20170301

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 9/00 20060101ALI20170223BHEP

Ipc: C22C 38/00 20060101AFI20170223BHEP

Ipc: B22F 1/02 20060101ALI20170223BHEP

Ipc: F01L 3/08 20060101ALI20170223BHEP

Ipc: C22C 1/04 20060101ALI20170223BHEP

Ipc: C22C 33/02 20060101ALI20170223BHEP

Ipc: B22F 5/00 20060101ALI20170223BHEP

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION HAS BEEN WITHDRAWN

17Q First examination report despatched

Effective date: 20191014

18W Application withdrawn

Effective date: 20191106