JPH03158444A - Valve seat made of fe-base sintered alloy excellent in wear resistance - Google Patents
Valve seat made of fe-base sintered alloy excellent in wear resistanceInfo
- Publication number
- JPH03158444A JPH03158444A JP29827289A JP29827289A JPH03158444A JP H03158444 A JPH03158444 A JP H03158444A JP 29827289 A JP29827289 A JP 29827289A JP 29827289 A JP29827289 A JP 29827289A JP H03158444 A JPH03158444 A JP H03158444A
- Authority
- JP
- Japan
- Prior art keywords
- valve seat
- sintered alloy
- based sintered
- wear resistance
- valve
- 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.)
- Pending
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 49
- 239000000956 alloy Substances 0.000 title claims abstract description 49
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 4
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract 2
- 229910052759 nickel Inorganic materials 0.000 claims abstract 2
- 239000002245 particle Substances 0.000 claims description 23
- 239000000758 substrate Substances 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 claims description 3
- 239000002184 metal Substances 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 11
- 238000002485 combustion reaction Methods 0.000 abstract description 7
- 239000000203 mixture Substances 0.000 abstract description 7
- 239000011159 matrix material Substances 0.000 abstract description 6
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 238000000034 method Methods 0.000 abstract description 2
- 229910052745 lead Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 34
- 230000000052 comparative effect Effects 0.000 description 12
- 230000008595 infiltration Effects 0.000 description 9
- 238000001764 infiltration Methods 0.000 description 9
- 239000000843 powder Substances 0.000 description 9
- 239000007789 gas Substances 0.000 description 8
- 239000010949 copper Substances 0.000 description 7
- 238000005245 sintering Methods 0.000 description 7
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 238000005728 strengthening Methods 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 239000011148 porous material Substances 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 229910021529 ammonia Inorganic materials 0.000 description 3
- 238000000354 decomposition reaction Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 229910017116 Fe—Mo Inorganic materials 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000007789 sealing Methods 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- MYMOFIZGZYHOMD-UHFFFAOYSA-N Dioxygen Chemical compound O=O MYMOFIZGZYHOMD-UHFFFAOYSA-N 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 125000002915 carbonyl group Chemical group [*:2]C([*:1])=O 0.000 description 1
- 238000010273 cold forging Methods 0.000 description 1
- 239000000567 combustion gas Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 229910001882 dioxygen Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910021382 natural graphite Inorganic materials 0.000 description 1
- 230000007935 neutral effect Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001294 propane Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、ディーゼルエンジンやガソリンエンジンな
どの内燃機関のうちでも特に高出力の内燃機関に適した
耐摩耗性に優れたＦｅＭｅ結合金製バルブシートに関す
るものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention provides a FeMe alloy valve with excellent wear resistance that is particularly suitable for high-output internal combustion engines such as diesel engines and gasoline engines. It concerns the seat.
従来、特開昭５８−１７８０７３号公報に記載されるよ
うに、重量％で（以下、％は重量％を示す。）、Ｍｏ：
０．１〜０．９％、 Ｎ１：０．５〜２．５％
。Conventionally, as described in JP-A-58-178073, Mo:
0.1-0.9%, N1: 0.5-2.5%
.
Ｃｏ：４．５〜７．５％、 Ｃｒ：３〜６．５
％。Co: 4.5-7.5%, Cr: 3-6.5
%.
Ｃ：０．５〜１．７％、 Ｗ：１〜２．７％。C: 0.5-1.7%, W: 1-2.7%.
を含有し、残りがＦｅと不可避不純物からなる組成を有
するＦｅ基合金素地に、
Ｃ：２〜３％、 Ｃｏニア〜１５％。2 to 3%, and 15% to 15% Co.
Ｗ ：１５〜２５％、Ｆｅ：１〜８％。W: 15-25%, Fe: 1-8%.
を含有し、残りがＣｒと不可避不純物からなる組成を有
するＣｒ基合金粒子と、Ｆｅ−Ｍｏ合金粒子：８〜１２
容量％。and Fe-Mo alloy particles: 8 to 12
capacity%.
が分散含有した組織並びに６〜１４容量％の気孔率を有
するＦｅ基焼結合金基体に、Ｃｕを溶浸してなる銅含浸
Ｆｅ基燃焼結合金製バルブシート知られている。A valve seat made of a copper-impregnated Fe-based sintered alloy is known, which is made by infiltrating Cu into a Fe-based sintered alloy base having a structure containing dispersed carbon dioxide and a porosity of 6 to 14% by volume.
しかし、最近の内燃機関は、過給機の採用、多弁化、高
速回転化などにより高出力化が計られて、熱的および機
械的負荷がますます増加する傾向があり、このような内
燃機関に上記従来の銅含浸Ｆｅ基燃焼結合金製バルブシ
ート装備すると、Ｆｅ基合金素地に分散するＣ「基合金
粒子およびＦｅ−Ｍｏ合金粒子は、硬質であるけれども
Ｆｅ基合金素地に対する密着性が悪く、内燃機関の作動
中にＦｅ基合金素地に分散するＣ「基合金粒子およびＦ
ｅ−Ｍｏ合金粒子は分離してバルブシート自体が摩耗し
、さらに、この分離した合金粒子は、相手部材であるバ
ルブをも摩耗せしめるという問題があった。However, recent internal combustion engines have been designed to achieve higher output through the use of superchargers, multiple valves, and higher rotation speeds, resulting in an increasing thermal and mechanical load. When equipped with the above-mentioned conventional copper-impregnated Fe-based combustion alloy valve seat, the C-based alloy particles and Fe-Mo alloy particles dispersed in the Fe-based alloy substrate have poor adhesion to the Fe-based alloy substrate, although they are hard. , C-based alloy particles and F-based alloy particles dispersed in the Fe-based alloy matrix during operation of the internal combustion engine.
There is a problem in that the e-Mo alloy particles are separated and the valve seat itself is worn out, and furthermore, the separated alloy particles also wear out the valve, which is a mating member.
そこで、本発明者らは、上述のような観点から、上記内
燃機関の高出力化に対しても十分に耐えることのできる
一段と優れた耐摩耗性を有するバルブシートを開発すべ
く研究を行った結果、Ｃｒ：０．５〜３％、
Ｍｏ： ０ 、５〜３％。Therefore, from the above-mentioned viewpoint, the present inventors conducted research to develop a valve seat that has even better wear resistance and can sufficiently withstand the increased output of the internal combustion engine. Result, Cr: 0.5-3%,
Mo: 0, 5-3%.
Ｎｌ：０．５〜３％、 Ｃｏ：２〜８％。Nl: 0.5-3%, Co: 2-8%.
ｃ ：０．８〜１．５％。c: 0.8-1.5%.
を含有し、残りがＦｅおよび不可避不純物からなる組成
並びにパーライト相およびベーナイト相を主体とした組
織からなるＦｅ基合金素地に、Ｃｒ：２５〜４５％、Ｗ
：２Ｑ〜３ｏ％。Cr: 25-45%, W
:2Q~3o%.
Ｃｏ：２０〜３０％、Ｃ：１〜３％。Co: 20-30%, C: 1-3%.
Ｓｌ：０．５〜２％、 Ｎｂ：０．２〜２％
。Sl: 0.5-2%, Nb: 0.2-2%
.
を含有し、残りがＦｅおよび不可避不純物からなる組成
を有する硬質粒子が１０〜２５％（以上重量％）分散し
た組織を有するＦｅ基焼結合金基体からなるバルブシー
トは耐摩耗性に優れており、上記要求に十分耐えること
ができるという知見を得たのである。The valve seat is made of an Fe-based sintered alloy base having a structure in which 10 to 25% (or more by weight) of hard particles are dispersed, with the remainder consisting of Fe and unavoidable impurities, and has excellent wear resistance. It was found that the above-mentioned requirements could be satisfactorily met.
この発明は、かかる知見に基づいてなされたものであっ
て、この発明は、上記組織を有するＦｅ基焼結合金基体
に、さらに、５〜２０重量％のＣｕを溶浸してなる銅含
浸Ｆｅ基焼結合金から構成してなるＦｅ基焼結合金製バ
ルブシートまたは５〜２０重量％のＰｂを溶浸してなる
鉛含浸Ｆｅ基焼結合金から構成してなるＦｅ基焼結合金
製バルブシートも含まれる。The present invention was made based on this knowledge, and the present invention is directed to a copper-impregnated Fe base formed by further infiltrating 5 to 20% by weight of Cu into an Fe-based sintered alloy base having the above-mentioned structure. A valve seat made of an Fe-based sintered alloy made of a sintered alloy or a valve seat made of an Fe-based sintered alloy made of a lead-impregnated Fe-based sintered alloy made by infiltrating 5 to 20% by weight of Pb is also available. included.
つぎに、この発明のバルブシートにおいて、これを構成
するＦｅ基焼結合金基体の組成を上記の通りに限定した
理由について説明する。Next, in the valve seat of the present invention, the reason why the composition of the Fe-based sintered alloy base constituting the valve seat is limited as described above will be explained.
Ａ、Ｆｅ基合金素地の成分限定理由
（ａ） Ｃ
Ｃ成分には、ＭＯおよびＣ「と結合して炭化物を形成し
、硬さを向上させる作用があるほか、パーライトおよび
ベーナイトを主体とする素地を形成して、耐摩耗性を向
上させる作用があるが、その含有量が０６５％未満では
上記作用に所望の効果が得られず、一方、その含有量が
１．５％を越えると、素地の硬さが高くなり、相手攻撃
性が増すようになることから、その含有量をＯ，Ｂ−１
，５％に定めた。A. Reason for limiting the components of the Fe-based alloy base (a) C The C component has the effect of combining with MO and C to form carbides and improving hardness, and also has the effect of improving the hardness of the base, which is mainly composed of pearlite and bainite. 0.065%, the desired effect cannot be obtained, and on the other hand, if the content exceeds 1.5%, it improves the abrasion resistance of the substrate. Since the hardness of B-1 increases and the aggressiveness of the opponent increases, its content is increased to O, B-1.
, set at 5%.
（ｂ） Ｃｒ
Ｃｒ成分には、素地に固溶して耐熱性を向上させる作用
があるほか炭化物を形成して耐摩耗性を向上させる作用
があるが、その含有量が０．５％未満では上記作用に所
望の効果が得られず、一方、その含有量が３％を越える
と、焼結性が劣化して高強度を確保することが困難にな
ることから、その含有量を０．５〜３％に定めた。(b) Cr Cr component has the effect of improving heat resistance by forming a solid solution in the base material, and also has the effect of forming carbide to improve wear resistance, but if its content is less than 0.5%, On the other hand, if the content exceeds 3%, the sinterability deteriorates and it becomes difficult to secure high strength, so the content is reduced to 0.5%. It was set at ~3%.
（ｃ） Ｍ。(c) M.
Ｍｏ成分には、素地に固溶して炭化物を形成し、耐摩耗
性を向上させる作用があるが、その含有量が０，５％未
満では上記作用に所望の効果が得られず、一方、その含
有量が３％を越えると、材料強度が低下することから、
その含有量を０．５〜３％に定めた。The Mo component forms a carbide in the base material and has the effect of improving wear resistance, but if its content is less than 0.5%, the desired effect cannot be obtained; If the content exceeds 3%, the strength of the material decreases.
Its content was set at 0.5-3%.
（ｄ） Ｎｌ
Ｎ１成分には、素地に固溶してこれを強化する作用があ
るが、その含有量が０．５％未満では上記作用に所望の
効果が得られず、一方、その含有量が３％を越えて含有
させても上記作用は飽和するだけであり、不経済である
ことから、その含有量を０．５〜３％に定めた。(d) Nl The N1 component has the effect of forming a solid solution in the base material and strengthening it, but if its content is less than 0.5%, the desired effect cannot be obtained from the above effect; Even if the content exceeds 3%, the above-mentioned effect will only be saturated and it is uneconomical, so the content was set at 0.5 to 3%.
（ｅ） Ｃ。(e) C.
Ｃｏ成分には、素地に固溶してこれを強化する作用があ
るが、その含有量が２％未満では上記作用に所望の効果
が得られず、一方、その含有量が８％を越えて含有させ
ても上記作用は飽和するだけであり、不経済であること
から、その含有量を２〜８％に定めた。The Co component has the effect of solidly dissolving in the base material and strengthening it, but if the content is less than 2%, the desired effect cannot be obtained from the above effect, while on the other hand, if the content exceeds 8% Even if it is contained, the above-mentioned effect is only saturated and it is uneconomical, so its content is set at 2 to 8%.
Ｂ、硬質粒子の成分限定理由
（ｒ） Ｃ
Ｃ成分には、炭化物を形成して硬質粒子を強化する作用
があるが、その含有量が１％未満では上記作用に所望の
効果が得られず、一方、その含有量が３％を越えると、
硬さが高くなりすぎ、相手攻撃性が増すようになること
から、その含有量を１〜３％に定めた。B. Reason for limiting the components of hard particles (r) C The C component has the effect of forming carbides and strengthening the hard particles, but if its content is less than 1%, the desired effect cannot be obtained from the above effect. , On the other hand, if its content exceeds 3%,
The content was set at 1 to 3% because the hardness would become too high and the opponent's aggressiveness would increase.
（ｇ） Ｃｒ
Ｃｒ成分には、硬質粒子の素地に固溶して耐熱性を向上
させる作用があるほか炭化物および金属間化合物を形成
して耐摩耗性を向上させる作用があるが、その含有量が
２５％未満では上記作用に所望の効果が得られず、一方
、その含有量が４５％を越えると、硬さの上昇を招き、
相手攻撃性が増加することから、その含有量を２５〜４
５％に定めた。(g) Cr The Cr component has the effect of improving heat resistance by forming a solid solution in the matrix of hard particles, and also has the effect of forming carbides and intermetallic compounds to improve wear resistance. If the content is less than 25%, the desired effect cannot be obtained, while if the content exceeds 45%, the hardness will increase.
Since it increases the opponent's aggressiveness, its content is increased to 25 to 4.
It was set at 5%.
（ｈ） Ｗ
Ｗ成分には、硬質粒子の素地中に炭化物および金属間化
合物を形成してｌｌｉｉＪＦｇ耗性を向上させる作用が
あるが、その含有量が２０％未満では上記作用に所望の
効果が得られず、一方、その含有量が３０％を越えると
、硬さの上昇を招き、相手攻撃性が増加することから、
その含有量を２５〜４５％に定めた。(h) W The W component has the effect of forming carbides and intermetallic compounds in the matrix of hard particles and improving the wear resistance of JFg, but if its content is less than 20%, the desired effect will not be achieved. On the other hand, if the content exceeds 30%, the hardness will increase and the opponent's aggressiveness will increase.
Its content was set at 25-45%.
（１） Ｎｂ
Ｎｂ成分には、炭化物を形成して硬質粒子の耐摩耗性を
向上させる作用および硬質粒子の素地に対する密着性を
強化する作用があるが、その含有量が０．２％未満では
上記作用に所望の効果が得られず、一方、その含有量が
２％を越えると、上記作用は飽和するだけであり、また
粉末アトマイズ時のぬれ性が低下するようになることか
ら、その含有量を０．２〜２％に定めた。(1) Nb The Nb component has the effect of forming carbides to improve the wear resistance of hard particles and the effect of strengthening the adhesion of hard particles to the substrate, but if its content is less than 0.2%, On the other hand, if the content exceeds 2%, the above action will only be saturated, and the wettability during powder atomization will decrease, so the content The amount was set at 0.2-2%.
（ｊ） Ｃ。(j) C.
Ｃｏ成分には、硬質粒子の素地に固溶してこれを強化す
る作用と耐熱性を向上させる作用があるが、その含有量
が２０％未満では上記作用に所望の効果が得られず、一
方、その含有量が３０％を越えて含有させても上記作用
は飽和するだけであり、不経済であることから、その含
有量を２０〜３０％に定めた。The Co component has the effect of solidly dissolving in the matrix of hard particles to strengthen it and improve heat resistance, but if its content is less than 20%, the desired effect cannot be obtained; If the content exceeds 30%, the above effect will only be saturated and it is uneconomical, so the content is set at 20 to 30%.
（ｋ） ５Ｉ
Ｓ１成分には、炭化物を形成して硬質粒子の耐摩耗性を
向上させる作用があるが、その含有量が０．２％未満で
は上記作用に所望の効果が得られず、一方、その含有量
が２％を越えると、硬質粒子を脆弱化するだけであるこ
とから、その含有量を０．２〜２％に定めた。(k) The 5I S1 component has the effect of forming carbides and improving the wear resistance of hard particles, but if its content is less than 0.2%, the desired effect cannot be obtained; If its content exceeds 2%, it will only weaken the hard particles, so its content was set at 0.2 to 2%.
Ｃ２硬質粒子の添加量
バルブシートに耐摩耗性を付与するためには、耐熱性を
有する素地耐摩耗性を有する硬質粒子を分散させる必要
があるがその添加量が１０％未満では上記作用に所望の
効果が得られず、一方、その添加量が２５％を越えると
、バルブシートの強度の低下およびバルブ攻撃性の増加
をもたらすことがらその添加量を１０〜２５％に定めた
。Addition amount of C2 hard particles In order to impart wear resistance to the valve seat, it is necessary to disperse hard particles that have wear resistance on the substrate that has heat resistance, but if the amount added is less than 10%, it is not possible to achieve the desired effect. However, if the amount added exceeds 25%, the strength of the valve seat decreases and the aggressiveness of the valve increases. Therefore, the amount added was set at 10 to 25%.
Ｄ、Ｃｕ溶浸量
この発明のバルブシートは、上記ＦＱ基焼結合金基体の
空孔に銅を溶浸せしめ、封孔による素地の強化と熱伝導
性の向上により耐熱性を向上させることもできるが、そ
の溶浸量が５％未満では上記作用に所望の効果が得られ
ず、一方、その溶浸量が２０％を越えて溶浸させるため
にはＦｅ基焼結合金基体の気孔率を上げなければならず
、Ｆｅ基焼結合金基体の気孔率を上げると得られたバル
ブシートの強度が低下することから、Ｃｕ溶浸量は５〜
２０％に定めた。D. Amount of Cu infiltration In the valve seat of the present invention, copper is infiltrated into the pores of the FQ-based sintered alloy base, and heat resistance can be improved by strengthening the base material by sealing the pores and improving thermal conductivity. However, if the amount of infiltration is less than 5%, the desired effect cannot be obtained in the above action.On the other hand, in order to infiltrate with the amount of infiltration exceeding 20%, the porosity of the Fe-based sintered alloy substrate must be adjusted. Increasing the porosity of the Fe-based sintered alloy substrate reduces the strength of the resulting valve seat, so the amount of Cu infiltration is
It was set at 20%.
Ｅ、Ｐｂ溶浸量
また、この発明のバルブシートは、上記Ｆｅ基焼結合金
基体の空孔に鉛を溶浸せしめ、封孔による素地の強化と
鉛のもつ自己潤滑性によりバルブ攻撃性を低下させるこ
ともできるが、その溶浸量が５％未満では上記作用に所
望の効果が得られず、一方、その溶浸量が２０％を越え
て溶浸させるためにはＦｅ基焼結合金基体の気孔率を上
げなければならず、Ｆｅ基焼結合金基体の気孔率を上げ
ると、得られたバルブシートの強度が低下することから
、Ｐｂ溶浸量は５〜２０％に定めた。E, Pb infiltration amount In addition, the valve seat of the present invention has lead infiltrated into the pores of the Fe-based sintered alloy base, thereby strengthening the base material by sealing the pores and reducing valve aggressiveness due to the self-lubricating property of lead. However, if the amount of infiltration is less than 5%, the desired effect cannot be obtained in the above action. The porosity of the base must be increased, and if the porosity of the Fe-based sintered alloy base is increased, the strength of the obtained valve seat will decrease, so the amount of Pb infiltration was set at 5 to 20%.
なお、この発明の耐摩耗性に優れたＦｅ基焼結合金製バ
ルブシートを製造するに際して、焼結は真空または還元
性ガス雰囲気中、温度＝１１００〜１２５０℃に１時間
保持の条件、Ｃｕ溶浸は、還元性ガス雰囲気中、温度：
１０９０−１１５０℃に２０分間保持の条件、Ｐｂ溶浸
は、中性ガス雰囲気中、温度＝５５０〜７００℃に１時
間保持の条件でそれぞれ実施し、さらに必要に応じて温
度＝５５０〜７５０℃に１時間保持の条件で熱処理を施
すのが望ましい。In manufacturing the valve seat made of Fe-based sintered alloy with excellent wear resistance of the present invention, sintering is carried out under the conditions of holding the temperature at 1100 to 1250°C for 1 hour in a vacuum or reducing gas atmosphere, and using Cu molten metal. Immersion in a reducing gas atmosphere, temperature:
Pb infiltration was carried out under the conditions of holding at 1090-1150°C for 20 minutes, and the temperature was held at 550-700°C for 1 hour in a neutral gas atmosphere, and if necessary, the temperature was 550-750°C. It is desirable to carry out the heat treatment under the condition of holding for 1 hour.
つぎに、この発明を実施例に基づいて具体的に説明する
。Next, the present invention will be specifically explained based on examples.
原料粉末として、いずれも粒度ニー １００メツシユの
Ｆｅ−１％Ｃ「粉末、Ｆｅ−３％Ｃ「粉末、カーボニル
粉末、Ｃｏ粉末、Ｍｏ粉末および天然黒鉛粉末を用意し
、さらに第１表に示される成分組成を６する硬質粒子を
用意し、これら原料粉末および硬質粒子を第１表に示さ
れるように配合し、混合した後、６〜６．５ｔ／ｃｊの
圧力で圧粉体にプレス成型し、この圧粉体を５００℃に
３０分間保持の条件で脱油したのち、アンモニア分解ガ
ス中、温度ニア００〜９００℃、３０分保持の条件で仮
焼結を行って仮焼結体を作製し、この仮焼結体を冷間鍛
造して密度を’１．Ｏｇ／ｃｒＡ以上にまで向上せしめ
たのち、再び脱油し、ついでアンモニア分解ガス中、温
度＝１１００〜１２５０℃、１時間保持の条件で焼結を
行い、必要に応じて、硬さの調整、組織の安定化のため
にアンモニア分解ガス中、温度＝５５０〜７５０℃、６
０分保持の熱処理を行い、外径： ３４ａｍ、内径：２
７龍、高さニア、２ｍｍの寸法をもった本発明Ｆｅ基焼
結合金製バルブシート以下、本発明バルブシートという
）１〜１５および比較Ｆｅ基焼結合金製バルブシート（
以下、比較バルブシートという）１〜１１を製造した。Fe-1% C powder, Fe-3% C powder, carbonyl powder, Co powder, Mo powder, and natural graphite powder, each with a particle size of 100 mesh, were prepared as raw material powders, and the powders were as shown in Table 1. Hard particles having a component composition of 6 are prepared, and these raw material powders and hard particles are blended as shown in Table 1, mixed, and then press-molded into a green compact at a pressure of 6 to 6.5 t/cj. After deoiling this compact by holding it at 500°C for 30 minutes, pre-sintering was performed in ammonia decomposition gas at a temperature of 00 to 900°C and holding it for 30 minutes to produce a temporary sintered body. Then, this pre-sintered body was cold-forged to increase the density to 1.0g/crA or more, then deoiled again, and then held in ammonia decomposition gas at a temperature of 1100 to 1250°C for 1 hour. Sintering is performed under the following conditions, and if necessary, sintering is performed in ammonia decomposition gas at a temperature of 550 to 750°C to adjust the hardness and stabilize the structure.
Heat treated for 0 minutes, outer diameter: 34am, inner diameter: 2
Valve seats made of Fe-based sintered alloy of the present invention having dimensions of 7 dragons, height near, and 2 mm (hereinafter referred to as the present invention valve seat) 1 to 15 and comparative valve seats made of Fe-based sintered alloy (hereinafter referred to as the present invention valve seat)
Nos. 1 to 11 (hereinafter referred to as comparative valve sheets) were manufactured.
また、本発明バルブシート３と同一寸法および同一成分
組成を有するが気孔率の異なったバルブシートを製造し
、これにメタン変成ガス雰囲気中、温度： １１１０℃
、２０分間保持の条件でＣｕ溶浸を行い、さらに大気中
、温度＝６２０℃、１時間保持の条件で焼戻しを行い、
本発明Ｃｕ溶浸Ｆｅ基焼結合金製バルブシート（以下、
本発明Ｃｕ溶浸バルブシートという） １８〜１８およ
び比較Ｃｕ溶浸Ｆｅ基焼結合金製バルブシート（以下、
比較Ｃｕ溶浸バルブシートという）１２を製造した。Further, a valve seat having the same dimensions and the same composition as the valve seat 3 of the present invention but having a different porosity was manufactured, and this was heated in a methane converted gas atmosphere at a temperature of 1110°C.
, Cu infiltration was performed under the conditions of holding for 20 minutes, and further tempering was performed under the conditions of holding in the air at a temperature of 620°C for 1 hour.
Valve seat made of the present invention Cu-infiltrated Fe-based sintered alloy (hereinafter referred to as
18 to 18 (referred to as the present invention Cu-infiltrated valve seat) and comparative Cu-infiltrated Fe-based sintered alloy valve seat (hereinafter referred to as
Comparative Cu-infiltrated valve seat) 12 was manufactured.
さらに、本発明バルブシート３と同一寸法および同一成
分組成を有するが気孔率の異なったバルブシートに、窒
素ガス雰囲気中、温度：６５０℃、１時間保持の条件で
Ｐｂ溶浸を行い、本発明Ｐｂ溶浸Ｆｅ基焼結合金製バル
ブシート（以下、本発明Ｐｂ溶浸バルブシートという）
１９〜２０および比較Ｐｂ溶浸Ｆｅ基焼結合金製バル
ブシート（以下、比較Ｐｂ溶浸バルブシートという）１
３を製造した。なお、比較バルブシート、比較Ｃｕ溶浸
バルブシートおよび比較Ｐｂ溶浸バルブシートは、いず
れも構成要件のうちいずれかがこの発明の条件から外れ
た値を持つものである（第１表において、この発明の条
件から外れた値を持つものに棗印を付した）。Further, a valve seat having the same dimensions and the same composition as the valve seat 3 of the present invention but having a different porosity was infiltrated with Pb in a nitrogen gas atmosphere at a temperature of 650°C and held for 1 hour. Valve seat made of Pb-infiltrated Fe-based sintered alloy (hereinafter referred to as the Pb-infiltrated valve seat of the present invention)
19 to 20 and comparative Pb-infiltrated Fe-based sintered alloy valve seat (hereinafter referred to as comparative Pb-infiltrated valve seat) 1
3 was manufactured. The comparative valve seat, the comparative Cu-infiltrated valve seat, and the comparative Pb-infiltrated valve seat each have a value that deviates from the conditions of this invention in any of the constituent elements (in Table 1, this Values that deviate from the conditions of the invention are marked with a date mark).
このようにして得られた各種バルブシートについて、下
記の条件で耐摩耗試験を行い、上記各種バルブシートの
最大摩耗深さを測定して耐摩耗性を評価し、さらにバル
ブの最大摩耗深さを測定してバルブ攻撃性を評価し、こ
れらの結果を第１表に示した。The various valve seats obtained in this way were subjected to wear resistance tests under the following conditions, and the maximum wear depth of the various valve seats was measured to evaluate the wear resistance, and the maximum wear depth of the valve was also measured. The valve aggressiveness was evaluated by measurements and the results are shown in Table 1.
耐摩耗試験条件
バルブ材質：５ＵＨ−３８、
バルブ加熱温度：９００℃、
バルブ着座回数ｓ ａｏｏｏ回／ｍ１ｎ、、雰 囲 気
：０．４ｋｇ／ｃ−のプロパンガスと流量１．８Ｎ
／ｓ１ｎ、の酸素ガスによる燃焼ガス、バルブシート加
熱温度（水冷）：２５０〜３００℃、着座荷重： ’ａ
ｏｋｇ。Wear resistance test conditions Valve material: 5UH-38, Valve heating temperature: 900℃, Valve seating number of times saooo times/m1n, Atmosphere: 0.4kg/c-propane gas and flow rate 1.8N
/s1n, combustion gas with oxygen gas, valve seat heating temperature (water cooling): 250-300℃, seating load: 'a
okay.
試験時間＝１００時間。Exam time = 100 hours.
第１表に示される結果から、本発明バルブシート１〜１
５、本発明Ｃｕ溶浸バルブシート１Ｂ〜１８および本発
明Ｐｂ溶浸バルブシート１９〜２０は、バルブシートの
摩耗が少なく、またバルブ攻撃性も低い値を示している
に対し、比較バルブシート１〜１１、比較Ｃｕ溶浸バル
ブシート１２および比較Ｐｂ溶浸バルブシート■３に見
られるように、この発明の条件から外れると上記特性の
うちいずれかの特性が劣ることが明らかであり、また従
来バルブシートの摩耗量も著しく大きいことがわかる。From the results shown in Table 1, the present invention valve sheets 1 to 1
5. Cu-infiltrated valve seats 1B to 18 of the present invention and Pb-infiltrated valve seats 19 to 20 of the present invention have less valve seat wear and low valve aggressiveness, whereas comparative valve seat 1 - 11, Comparative Cu-infiltrated valve seat 12 and Comparative Pb-infiltrated valve seat 3, it is clear that any of the above characteristics will be inferior if the conditions of the present invention are not met. It can be seen that the amount of wear on the valve seat is also significantly large.
上述のように、この発明のＦｅ基焼結合金製バルブシー
トは、優れた耐摩耗性と低いバルブ攻撃性を有しており
、高出力内燃機関のバルブシートとして長期にわたって
著しく優れた性能を発揮する。As mentioned above, the Fe-based sintered alloy valve seat of the present invention has excellent wear resistance and low valve aggressiveness, and exhibits outstanding long-term performance as a valve seat for high-output internal combustion engines. do.
なお、上記実施例では、この発明の耐摩耗性に優れたＦ
ｅ基焼結合金製バルブシートを製造する方法として仮焼
結したのち冷間鍛造して得られた冷間鍛造材を焼結する
製造法を採用しているが、製造法としては上記実施例記
載の方法に限定されるものではなく、１次焼結したのち
熱間鍛造して得られた熱間鍛造材を２次焼結する製造法
、圧粉体を焼結する通常の製造法なども採用することが
できる。In addition, in the above example, F
As a method of manufacturing a valve seat made of e-based sintered alloy, a manufacturing method is adopted in which a cold forged material obtained by pre-sintering and then cold forging is sintered. It is not limited to the methods described, but includes a manufacturing method in which a hot forged material obtained by primary sintering and then hot forging is subjected to secondary sintering, a normal manufacturing method in which a green compact is sintered, etc. can also be adopted.
出願入量 三菱金属株式会社Application intake Mitsubishi Metals Co., Ltd.
Claims (3)
：０．５〜３％、Ｃｏ：２〜８％、 Ｃ：０．６〜１．５％、 を含有し、残りがＦｅおよび不可避不純物からなる組成
並びにパーライト相およびベーナイト相を主体とした組
織からなるＦｅ基合金素地に、Ｃｒ：２５〜４５％、Ｗ
：２０〜３０％、 Ｃｏ：２０〜３０％、Ｃ：１〜３％、 Ｓｉ：０．５〜２％、Ｎｂ：０．２〜２％、を含有し、
残りがＦｅおよび不可避不純物からなる組成を有する硬
質粒子が１０〜２５％（以上重量％）分散した組織を有
するＦｅ基焼結合金基体からなることを特徴とする耐摩
耗性に優れたＦｅ基焼結合金製バルブシート。(1) Cr: 0.5-3%, Mo: 0.5-3%, Ni
:0.5 to 3%, Co: 2 to 8%, C: 0.6 to 1.5%, with the remainder consisting of Fe and unavoidable impurities, and a structure mainly consisting of pearlite and bainite phases. Fe-based alloy base consisting of Cr: 25-45%, W
: 20-30%, Co: 20-30%, C: 1-3%, Si: 0.5-2%, Nb: 0.2-2%,
A Fe-based sintered alloy substrate with excellent wear resistance characterized by being composed of an Fe-based sintered alloy base having a structure in which 10 to 25% (or more by weight) of hard particles are dispersed, the remainder being Fe and unavoidable impurities. Bonded metal valve seat.
重量％のＣｕを溶浸してなる銅含浸Ｆｅ基焼結合金から
構成してなることを特徴とする耐摩耗性に優れたＦｅ基
焼結合金製バルブシート。(2) The Fe-based sintered alloy substrate according to claim 1 has 5 to 20
A valve seat made of a Fe-based sintered alloy with excellent wear resistance, characterized in that it is made of a copper-impregnated Fe-based sintered alloy formed by infiltrating Cu in the amount of % by weight.
重量％のＰｂを溶浸してなる鉛含浸Ｆｅ基焼結合金から
構成してなることを特徴とする耐摩耗性に優れたＦｅ基
焼結合金製バルブシート。(3) The Fe-based sintered alloy substrate according to claim 1 has 5 to 20
A valve seat made of a Fe-based sintered alloy with excellent wear resistance, characterized in that it is made of a lead-impregnated Fe-based sintered alloy formed by infiltrating Pb in an amount of % by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29827289A JPH03158444A (en) | 1989-11-16 | 1989-11-16 | Valve seat made of fe-base sintered alloy excellent in wear resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29827289A JPH03158444A (en) | 1989-11-16 | 1989-11-16 | Valve seat made of fe-base sintered alloy excellent in wear resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03158444A true JPH03158444A (en) | 1991-07-08 |
Family
ID=17857490
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP29827289A Pending JPH03158444A (en) | 1989-11-16 | 1989-11-16 | Valve seat made of fe-base sintered alloy excellent in wear resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03158444A (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5512080A (en) * | 1992-11-27 | 1996-04-30 | Toyota Jidosha Kabushiki Kaisha | Fe-based alloy powder adapted for sintering, Fe-based sintered alloy having wear resistance, and process for producing the same |
| JPH09287422A (en) * | 1996-04-25 | 1997-11-04 | Nippon Piston Ring Co Ltd | Manufacture for sintered alloy connection type valve sheet and connection type valve sheet sintered alloy material |
| FR2765269A1 (en) * | 1997-06-27 | 1998-12-31 | Nippon Piston Ring Co Ltd | VALVE SEAT FOR INTERNAL COMBUSTION ENGINE |
| WO1999025889A1 (en) * | 1997-11-14 | 1999-05-27 | Mitsubishi Materials Co. | VALVE SEAT MADE OF Fe-BASE SINTERED ALLOY EXCELLENT IN WEAR RESISTANCE |
| JP2000144351A (en) * | 1998-11-18 | 2000-05-26 | Mitsubishi Materials Corp | Valve seat made of iron-base sintered alloy and its manufacture |
| JP2000226644A (en) * | 1999-02-04 | 2000-08-15 | Mitsubishi Materials Corp | HIGH STRENGTH Fe BASE SINTERED VALVE SEAT AND ITS PRODUCTION |
| KR100349762B1 (en) * | 2000-03-31 | 2002-08-22 | 현대자동차주식회사 | A compound of abrasion proof sintered alloy for valve seat and its preparing method |
-
1989
- 1989-11-16 JP JP29827289A patent/JPH03158444A/en active Pending
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5512080A (en) * | 1992-11-27 | 1996-04-30 | Toyota Jidosha Kabushiki Kaisha | Fe-based alloy powder adapted for sintering, Fe-based sintered alloy having wear resistance, and process for producing the same |
| JPH09287422A (en) * | 1996-04-25 | 1997-11-04 | Nippon Piston Ring Co Ltd | Manufacture for sintered alloy connection type valve sheet and connection type valve sheet sintered alloy material |
| FR2765269A1 (en) * | 1997-06-27 | 1998-12-31 | Nippon Piston Ring Co Ltd | VALVE SEAT FOR INTERNAL COMBUSTION ENGINE |
| WO1999025889A1 (en) * | 1997-11-14 | 1999-05-27 | Mitsubishi Materials Co. | VALVE SEAT MADE OF Fe-BASE SINTERED ALLOY EXCELLENT IN WEAR RESISTANCE |
| JP2000144351A (en) * | 1998-11-18 | 2000-05-26 | Mitsubishi Materials Corp | Valve seat made of iron-base sintered alloy and its manufacture |
| JP2000226644A (en) * | 1999-02-04 | 2000-08-15 | Mitsubishi Materials Corp | HIGH STRENGTH Fe BASE SINTERED VALVE SEAT AND ITS PRODUCTION |
| KR100349762B1 (en) * | 2000-03-31 | 2002-08-22 | 현대자동차주식회사 | A compound of abrasion proof sintered alloy for valve seat and its preparing method |
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