WO2005038065A1 - Feuille de soupape en alliage fritte de fe-al-c possedant une excellente resistance a l'oxydation a une temperature elevee et une grande resistance mecanique - Google Patents

Feuille de soupape en alliage fritte de fe-al-c possedant une excellente resistance a l'oxydation a une temperature elevee et une grande resistance mecanique Download PDF

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Publication number
WO2005038065A1
WO2005038065A1 PCT/JP2004/015121 JP2004015121W WO2005038065A1 WO 2005038065 A1 WO2005038065 A1 WO 2005038065A1 JP 2004015121 W JP2004015121 W JP 2004015121W WO 2005038065 A1 WO2005038065 A1 WO 2005038065A1
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WO
WIPO (PCT)
Prior art keywords
phase
sintered
alloy
sintered alloy
valve seat
Prior art date
Application number
PCT/JP2004/015121
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English (en)
Japanese (ja)
Inventor
Koichiro Morimoto
Kunio Hanata
Takashi Nishida
Tomohiro Sakai
Original Assignee
Mitsubishi Materials Pmg Corporation
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 Mitsubishi Materials Pmg Corporation filed Critical Mitsubishi Materials Pmg Corporation
Publication of WO2005038065A1 publication Critical patent/WO2005038065A1/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
    • C22C33/0278—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
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

Definitions

  • Valve seat made of sintered Fe-A1-C alloy with excellent high-temperature resistance to oxidation and high strength
  • the present invention has excellent high-temperature oxidation resistance and high strength, and exhibits excellent wear resistance over a long period of time, particularly when incorporated in an engine of an LP gas vehicle that is a low-emission vehicle.
  • valve seats made of an Fe-based sintered alloy have been proposed as valve seats for various types of automobile engines, and among them, in terms of mass% (hereinafter,% indicates mass%),
  • the above-mentioned conventional valve seat made of a sintered Fe-A1-C alloy can be used under normal conditions, that is, in an atmosphere of ammonia decomposition gas or RX decomposition gas at a temperature of 1050-1150 ° C. Even if sintering for 2 hours, a sintered body with a specified strength is manufactured due to the poor sinterability of the powders of Fe powder, A1 powder and carbon powder used as raw material powders. Therefore, the raw material powder is blended into a predetermined composition, mixed, and press-formed into a green compact at a current density of 5 to 100 AZmm2 by current press molding sintering (press pressure is usually lOOMPa).
  • Patent Document 1 JP-A-2002-146495
  • Patent Document 2 JP 2002-146496
  • the valve seat made of the conventional Fe-A1-C sintered alloy has a two-phase mixed structure and a three-phase mixed structure as described above, and has the Fe-C phase of the constituent phases. Is inferior to high-temperature oxidation resistance, and particularly when incorporated in an engine of an LP gas vehicle, the high-temperature low exhaust gas causes the oxidation of the Fe—C phase to proceed relatively quickly, Wear is accelerated by the cause, and in the case of the two-phase mixed structure and the three-phase mixed structure, the strength of the phase boundary is low due to insufficient sinterability, so that it is sufficient for thinning and diameter reduction. Strength cannot be secured.
  • the green compact obtained by blending with the blending composition of the above, mixing under normal conditions, and press-molding, in a vacuum, preferably in a vacuum of lOPa or less, is relatively higher than the normal sintering temperature described above!
  • the manufactured valve seats completely dissolve Fe-A1 alloy and carbon (C) in Fe during sintering.
  • the valve seat made of a Fe—A1—C solid solution has a Fe—A1—C solid solution single phase structure.
  • the research results show that the results will be further improved.
  • Excellent high-temperature oxidation resistance and high strength composed of Fe-A1-C sintered alloy with Fe-A1-C solid solution single-phase structure, with the composition containing iron and the balance being Fe and inevitable impurity power It is characterized by a valve seat made of a sintered Fe-A1-C alloy having the following characteristics.
  • the Fe—A1—C solid solution single phase structure of the Fe—A1—C sintered alloy constituting the valve seat of the present invention includes Fe powder, Fe—Al alloy powder, and carbon (C) as raw material powders. It can be formed by using powder, limiting the content ratio of A1 and C as described above, and performing high-temperature vacuum sintering, and has higher strength and strength because the phase boundary does not exist.
  • the Fe—A1-C solid solution itself which is hardly colored, also has the strength of the Fe component, the high-temperature oxidation resistance of the A1 component, and the hardness by the action of the C component.
  • the content of the A1 component is less than 20%, the desired excellent high-temperature oxidation resistance cannot be secured, while if the content exceeds 30%, the Fe-A1 alloy powder as the raw material powder is blended. If the ratio becomes too large, it becomes difficult to completely dissolve in Fe at the time of sintering, and a two-phase mixed structure and a three-phase mixed structure that cause deterioration in strength and high-temperature oxidation resistance will appear. Therefore, the content ratio of A1 component was determined to be 20-30%. (b) C
  • the C component which is a Fe—Al—C solid solution, has the effect of improving its hardness and thereby improving the wear resistance of the valve sheet, but is desirable if its content is less than 0.5%.
  • the content ratio exceeds 1.5%, complete solid solution in Fe during sintering becomes difficult as in the case of A1, and a two-phase mixed structure and three-phase
  • the content and the content of the C component were determined to be 0.5 to 1.5% because the mixed structure resulted in a rapid decrease in strength and high-temperature oxidation resistance.
  • the valve seat made of a sintered Fe—A1—C alloy of the present invention is composed of a sintered Fe—A1—C alloy having a single phase structure of a solid solution of Fe—A1—C. Because the phase structure has excellent high-temperature oxidation resistance and high strength, especially when incorporated into the engine of an LP gas vehicle, which is a low-emission vehicle, the exhaust gas power S800 — Despite reaching a high temperature of 900 ° C, it exhibits excellent abrasion resistance over a long period of time, and enables thinning and small diameter molding.
  • valve seat made of a sintered Fe—A1-C alloy of the present invention will be specifically described with reference to examples.
  • the mixture was blended in the composition shown in 1 and 0.8% of zinc stearate was added as a binder to the above-mentioned blended powder at a ratio of 0.8% and mixed with a mixer for 30 minutes.
  • Fe powder having an average particle size of 5 ⁇ m, A1 powder having an average particle size of 20 ⁇ m, and carbon (C) powder having an average particle size of 10 m were used as raw material powders.
  • the raw material powder was blended into the blending composition shown in Table 1, 0.8% zinc stearate was added as a binder to the blended powder at a ratio of 0.8%, and the mixture was mixed with a mixer for 30 minutes.
  • the structures of the sintered valve seat 117 of the present invention and the conventional sintered valve seat 117 obtained as a result were observed using a metallographic microscope.
  • the sintered valve seat 117 shows a single-phase structure of the Fe—A1—C solid solution with a deviation
  • the conventional sintered valve seat 117 has a two-phase mixed structure of the Fe—A1 alloy phase and the Fe—C phase. Or, it showed a three-phase mixed structure of Fe-A1 alloy phase, Fe-C phase and carbon (C) phase.
  • Table 1 also shows the results of measuring the radial crushing strength for the purpose of evaluating the strength. Table 1 also shows the Vickers hardness.
  • the sintered valve seat 117 of the present invention and the conventional sintered valve seat 117 are assembled into an engine of an LP gas vehicle having a displacement of 5000 cc, respectively.
  • Counterpart material valve: JIS ⁇ SUH35 (heat resistant steel) body with stellite 12 overlaid with lmm thickness,
  • the sintered valve seat 117 of the present invention made of Fe-A1-C sintered bond gold having a single-phase structure of Fe-A1-C solid solution has the above-mentioned Fe — A1— C solid solution
  • the single-phase structure has excellent high-temperature oxidation resistance, so when it is incorporated into the engine of an LP gas vehicle, which is a low-emission vehicle, it is accompanied by high-speed driving and high output of the vehicle.
  • the exhaust gas reaches a high temperature of 800-900 ° C, it exhibits extremely low aggressiveness and excellent wear resistance over a long period of time.
  • the valve seat made of a sintered Fe—A1-C alloy according to the present invention can be used not only for a gasoline engine and a diesel engine, but also for a high speed and high output of an automobile. Has reached a high temperature of 800-900 ° C and has low exhaust gas, so the contact between the valve seat and valve takes the form of direct metal-to-metal contact. In such a case, excellent wear resistance is exhibited over a long period of time, and since it has high strength, it is possible to reduce the thickness and diameter of the vehicle. And it can respond satisfactorily to miniaturization.

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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

L'objectif de l'invention est d'obtenir une feuille de soupape en alliage fritté de Fe-Al-C qui fasse preuve d'une excellente résistance à l'oxydation à une température élevée et d'une grande résistance mécanique. L'invention concerne donc plus spécifiquement une feuille de soupape en alliage fritté Fe-Al-C qui comprend un alliage fritté de Fe-Al-C dont la composition chimique, en % en masse, est de 20 à 30 % de Al, 0,5 à 1,5 % de C, le reste étant constitué de Fe et d'inévitables impuretés. Cet alliage possède en outre une structure de phase unique de solution solide Fe-Al-C.
PCT/JP2004/015121 2003-10-16 2004-10-14 Feuille de soupape en alliage fritte de fe-al-c possedant une excellente resistance a l'oxydation a une temperature elevee et une grande resistance mecanique WO2005038065A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2003355917A JP2005120416A (ja) 2003-10-16 2003-10-16 すぐれた高温耐酸化性と高強度を有するＦｅ−Ａｌ−Ｃ焼結合金製バルブシート
JP2003-355917 2003-10-16

Publications (1)

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WO2005038065A1 true WO2005038065A1 (fr) 2005-04-28

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PCT/JP2004/015121 WO2005038065A1 (fr) 2003-10-16 2004-10-14 Feuille de soupape en alliage fritte de fe-al-c possedant une excellente resistance a l'oxydation a une temperature elevee et une grande resistance mecanique

Country Status (2)

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JP (1) JP2005120416A (fr)
WO (1) WO2005038065A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180142331A1 (en) * 2016-11-10 2018-05-24 U.S. Army Research Laboratory Attn: Rdrl-Loc-I Cemented carbide containing tungsten carbide and finegrained iron alloy binder

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100742689B1 (ko) 2005-08-03 2007-07-25 나태엽 내열강 합금소재 제조방법

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001011591A (ja) * 1999-07-01 2001-01-16 Mitsubishi Materials Corp 軽量で高温耐摩耗性および熱伝導性のすぐれたピストンリング耐摩環
JP2002146496A (ja) * 2000-11-08 2002-05-22 Mitsubishi Materials Corp 相手攻撃性が小さくかつ切削性に優れた鉄アルミナイド基燒結合金及びその製造方法

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001011591A (ja) * 1999-07-01 2001-01-16 Mitsubishi Materials Corp 軽量で高温耐摩耗性および熱伝導性のすぐれたピストンリング耐摩環
JP2002146496A (ja) * 2000-11-08 2002-05-22 Mitsubishi Materials Corp 相手攻撃性が小さくかつ切削性に優れた鉄アルミナイド基燒結合金及びその製造方法

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180142331A1 (en) * 2016-11-10 2018-05-24 U.S. Army Research Laboratory Attn: Rdrl-Loc-I Cemented carbide containing tungsten carbide and finegrained iron alloy binder
US11434549B2 (en) 2016-11-10 2022-09-06 The United States Of America As Represented By The Secretary Of The Army Cemented carbide containing tungsten carbide and finegrained iron alloy binder
US20230160042A1 (en) * 2016-11-10 2023-05-25 U.S. Army Research Laboratory Attn: Rdrl-Loc-I Cemented carbide containing tungsten carbide and fine grained iron alloy binder
US11725262B2 (en) * 2016-11-10 2023-08-15 The United States Of America As Represented By The Secretary Of The Army Cemented carbide containing tungsten carbide and fine grained iron alloy binder

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