JPS62188758A - Ferrous sintered alloy for valve seat - Google Patents
Ferrous sintered alloy for valve seatInfo
- Publication number
- JPS62188758A JPS62188758A JP23073186A JP23073186A JPS62188758A JP S62188758 A JPS62188758 A JP S62188758A JP 23073186 A JP23073186 A JP 23073186A JP 23073186 A JP23073186 A JP 23073186A JP S62188758 A JPS62188758 A JP S62188758A
- Authority
- JP
- Japan
- Prior art keywords
- iron
- alloy
- carbon
- balance
- sintered 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.)
- Pending
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 42
- 239000000956 alloy Substances 0.000 title claims abstract description 42
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 title claims abstract description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 36
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 18
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052742 iron Inorganic materials 0.000 claims abstract description 10
- 239000011159 matrix material Substances 0.000 claims abstract description 9
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 9
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 239000002245 particle Substances 0.000 claims description 27
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 19
- 239000011651 chromium Substances 0.000 claims description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 17
- 239000010955 niobium Substances 0.000 claims description 17
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 7
- 229910052758 niobium Inorganic materials 0.000 claims description 7
- 229910017052 cobalt Inorganic materials 0.000 claims description 6
- 239000010941 cobalt Substances 0.000 claims description 6
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 6
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 6
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 6
- 239000010937 tungsten Substances 0.000 claims description 6
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 5
- 239000000463 material Substances 0.000 abstract description 8
- 239000000203 mixture Substances 0.000 abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 abstract description 3
- 230000000694 effects Effects 0.000 description 11
- 230000013011 mating Effects 0.000 description 5
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 230000008595 infiltration Effects 0.000 description 4
- 238000001764 infiltration Methods 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 239000002131 composite material Substances 0.000 description 3
- 229910001018 Cast iron Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910021529 ammonia Inorganic materials 0.000 description 2
- 238000000354 decomposition reaction Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 229910000531 Co alloy Inorganic materials 0.000 description 1
- 241000219122 Cucurbita Species 0.000 description 1
- 235000009852 Cucurbita pepo Nutrition 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- FHKPLLOSJHHKNU-INIZCTEOSA-N [(3S)-3-[8-(1-ethyl-5-methylpyrazol-4-yl)-9-methylpurin-6-yl]oxypyrrolidin-1-yl]-(oxan-4-yl)methanone Chemical compound C(C)N1N=CC(=C1C)C=1N(C2=NC=NC(=C2N=1)O[C@@H]1CN(CC1)C(=O)C1CCOCC1)C FHKPLLOSJHHKNU-INIZCTEOSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- -1 but in this case Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 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）
本発明は内燃機関のバルブシート用焼結合金に係り、よ
シ詳しくはバルブシート自身の耐摩耗性を向上させ、相
手パルプへの攻撃性を低減させ得るような焼結合金に関
するものである。Detailed Description of the Invention (Field of Industrial Application) The present invention relates to a sintered alloy for valve seats of internal combustion engines, and more specifically, it improves the wear resistance of the valve seats themselves and reduces the aggressiveness of the mating pulp. This relates to a sintered alloy that can reduce the
（従来技術） 最近、自動車用エンジンは高出力、高回転化。(Conventional technology) Recently, automobile engines have become more powerful and rotated at higher speeds.
排ガス対策や燃費対策を施される傾向にある。There is a tendency for exhaust gas and fuel efficiency measures to be implemented.
そうした場合、パルプ及びバルブシート部品は従来以上
に厳しい条件にさらされることになる。In such a case, the pulp and valve seat components will be exposed to more severe conditions than before.
従来自動車用エンジンのバルブシートには鉄系焼結合金
、耐熱鋼、鋳鉄が使用されている。特に高温での耐摩耗
性を高めるため、クロム、ニッケル、コバルト、モリブ
デン等の合金用元素を添加した鉄系焼結合金が多用され
ククある。Conventionally, ferrous sintered alloys, heat-resistant steel, and cast iron have been used for the valve seats of automobile engines. In order to improve wear resistance, especially at high temperatures, iron-based sintered alloys to which alloying elements such as chromium, nickel, cobalt, and molybdenum are added are often used.
（発明が解決しようとする問題点）
しかしそうした７エロモリブデン等の金属間化合物とか
複合炭化物を添加して極度に耐摩耗性を高めたバルブシ
ートをそのまま使用すると相手パルプの摩耗を増大させ
るという欠点があったＯ
本発明は上記問題点に鑑みなされたもので、その目的と
するところは、耐摩耗性が特に高められていない通常の
汎用エンジンパルプ（例えばＪＩ８ ＮＰＣ７５１製）
を相手にした場合にも相手材を摩耗させず且つバルブシ
ート自身の耐摩耗性にも優れた、言い換えるならパルプ
機構全体の耐久性を向上できるようなバルブシート用合
金を得ようとするものである。(Problem to be solved by the invention) However, if a valve seat that has been added with intermetallic compounds such as 7eromolybdenum or composite carbide to have extremely high wear resistance is used as is, it will increase the wear of the mating pulp. The present invention was made in view of the above problems, and its purpose is to use ordinary general-purpose engine pulp (such as JI8 NPC751) that does not have particularly enhanced wear resistance.
The aim is to obtain an alloy for valve seats that does not wear out the other material and has excellent wear resistance of the valve seat itself, in other words, can improve the durability of the entire pulp mechanism. be.
（問題点を解決するための手段）
そのため、本発明のバルブシート用鉄系焼結合金は、重
量比で、クロム（Ｃｒ） １０〜７０％、タングステ
ン（Ｗ）５〜２０９％、バナジウム（Ｖ）又はニオブ（
Ｎｂ）の１種又は２種２〜２０％、鉄（Ｆｅ）ｚｏ１以
下、炭素（Ｃ）（１５〜３％及び残部コバルト（Ｃｏ）
から成るコバルト合金粒子５〜２５〜を、炭素（Ｃ）１
５〜２％、所望によりニッケル（Ｎｉ）１〜１０チ及び
残部鉄（Ｆｅ）と不可避不純物からなるパーライトを主
体の素地中に分散させたことを特徴とする。(Means for Solving the Problems) Therefore, the iron-based sintered alloy for valve seats of the present invention contains, by weight, 10 to 70% chromium (Cr), 5 to 209% tungsten (W), and vanadium (V ) or niobium (
2-20% of one or two types of Nb), iron (Fe) zo1 or less, carbon (C) (15-3% and the balance cobalt (Co))
Cobalt alloy particles 5 to 25 consisting of carbon (C) 1
It is characterized in that pearlite consisting of 5 to 2%, optionally 1 to 10 nickel (Ni), and the balance iron (Fe) and inevitable impurities is dispersed in the main matrix.
また、本発明は前記焼結合金に鉛（Ｐｂ） １〜２０チ
を溶浸したことを特徴とする。Further, the present invention is characterized in that the sintered alloy is infiltrated with 1 to 20 pieces of lead (Pb).
なお、本発明において−は特記しないかぎり重量％を示
す。In the present invention, - indicates weight % unless otherwise specified.
本発明で用いる各成分元素の限定理由について説明する
。The reason for limiting each component element used in the present invention will be explained.
まず、硬質粒子として加える合金粒子の各成分元素につ
いて説明する。First, each component element of the alloy particles added as hard particles will be explained.
合金粒子中のＣｒ （クロム）はＣ（炭素）と化合して
炭化物を形成するとともに一部がＣ。Cr (chromium) in the alloy particles combines with C (carbon) to form carbides, and some of them are carbon.
と付会を形成し合金粒子の硬さを向上させる効果を有し
ているが、Ｃｒが１０％未満では上記の効果が不十分で
あり、７０チを超えるとＣｒ の拡散が周囲の基地へ進
み過ぎ、合金粒子の内部及び周縁に空隙を生じ、合金粒
子がもろくなる。However, if the Cr content is less than 10%, the above effect is insufficient, and if it exceeds 70%, Cr will diffuse into the surrounding bases. If it advances too much, voids are created inside and at the periphery of the alloy particles, and the alloy particles become brittle.
そのためＣｒは１０〜７０−と限定した。Therefore, Cr was limited to 10 to 70-.
Ｗ（タングステン）は、Ｃと化合してＭＣｆｉの硬質炭
化物とＣｏ との複炭化物を形成し、合金粒子の硬さを
向上させるが、Ｗが５〜未満ではその効果が発揮されず
、２０−を超えると合金粒子が硬くなシ過ぎ、相手材で
あるパルプへの攻撃性が増大するため、Ｗは５〜２０９
Ｇとした。W (tungsten) combines with C to form a double carbide of MCfi hard carbide and Co and improves the hardness of the alloy particles, but if W is less than 5 or more, the effect is not exhibited, and 20- If W exceeds 5 to 209, the alloy particles will become too hard and will be more aggressive towards the other material, pulp.
It was set as G.
■（バナジウム）やＮｂにニオブ）は炭素と化合して炭
化物を形成し硬質粒子の硬さを向上させると同時に、硬
質粒子中にて他のＣｒ−？Ｗの炭化物と一緒罠なって複
合炭化物の粒子を形成するが、その場合■やＮｂの入っ
た複合炭化物粒子は微細化する性質を有するのでｂ Ｖ
＋Ｎｂは相手パルプ攻撃性を低減させる効果を有する。■(vanadium), Nb and niobium) combine with carbon to form carbides and improve the hardness of hard particles, while at the same time, other Cr-? W traps with carbide to form composite carbide particles, but in this case, composite carbide particles containing ■ and Nb have the property of becoming finer, so b V
+Nb has the effect of reducing the aggressiveness of the opponent pulp.
そしてこれら両金属の合計量が２％以下ではその効果が
なく、２０％以上では硬くなりすぎ相手パルプを攻撃す
る。そのためＶ ＋ Ｎｂ は２〜２０チとした。If the total amount of these two metals is less than 2%, there is no effect, and if it is more than 20%, the pulp becomes too hard and attacks the other pulp. Therefore, V + Nb was set to 2 to 20 inches.
硬質粒子中のＣ（炭素）はＯｒ、 ｗ、 Ｖ、 Ｎｂと
化合して炭化物を形成して硬質粒子の硬さを向上させる
が、α５チ以下ではその効果がなく、３−を超えると炭
化物量が多すぎてもろくなる。C (carbon) in the hard particles combines with Or, W, V, and Nb to form carbides and improve the hardness of the hard particles, but if α5 or less, there is no effect, and if α exceeds 3-, carbides are formed. Too much will make it brittle.
そのため、Ｃは１５〜３−とじた。Therefore, C was closed at 15-3.
Ｆｅ （鉄）は特に添加しなくてもよいが、バルブシ
ートに必要とする強度等に問題がなければ、高価なＣｏ
０代わシに２０−以下の任意の範囲で用いることができ
る。また、Ｃｒ、 Ｗ、 Ｍ。It is not necessary to add Fe (iron), but if there is no problem with the strength required for the valve seat, expensive Co
Instead of 0, it can be used in any range of 20 or less. Also, Cr, W, M.
を単体としてではなく７エロアロイとして合金の原料に
用いる場合に添加されることになる。It is added when used as a raw material for an alloy not as a single substance but as a 7Eroalloy.
合金粒子は耐摩耗性の向上に効果があることから用いら
れる。その粒径は３０〜１５０７ｍが好ましく、合金中
のＣＯの一部が基地中に拡散して粒子の周囲に拡散層を
形成することによって、粒子と基地との結合力が増し、
該粒子の脱落が防止される。該合金粒子は５ｓ未満では
得られる焼結合金の耐摩耗効果が発揮されず、２５〜を
超えると成形性、圧縮性及び被剛性が低下するとともに
相手材であるパルプへの攻撃性が増大するため、合金粒
子は５〜２５〜と限定した。Alloy particles are used because they are effective in improving wear resistance. The particle size is preferably 30 to 1507 m, and a part of the CO in the alloy diffuses into the matrix to form a diffusion layer around the particles, increasing the bonding force between the particles and the matrix.
The particles are prevented from falling off. If the alloy particles are less than 5 seconds, the wear-resistant effect of the obtained sintered alloy will not be exhibited, and if it exceeds 25 seconds, the formability, compressibility, and stiffness will decrease and the attack on the pulp, which is the mating material, will increase. Therefore, the number of alloy particles was limited to 5 to 25.
次に基地について説明する。Next, I will explain about the base.
Ｃ（炭素）は基地のＦｅに固溶して硬さを向上させると
共に硬質粒子中のＣｒ、 ｗ、 Ｖｅ Ｎｂと化合して
硬質の炭化物を構成し硬質粒子の硬さをさらに向上させ
る効果があるが、α５〜以下ではその効果がなく、２チ
以上ではセメンタイトが析出して基地が脆化したり、遊
離黒鉛が多量に残留しすぎて基地の強度が低下するため
Ｃは（１５〜２−とした。C (carbon) improves the hardness by solidly dissolving in Fe in the matrix, and also combines with Cr, w, Ve, Nb in the hard particles to form hard carbide, which has the effect of further improving the hardness of the hard particles. However, if it is less than α5, it has no effect, and if it is more than 2, cementite will precipitate and the base will become brittle, or too much free graphite will remain, reducing the strength of the base. And so.
Ｎｉにッケル）はＦｅ基地に固溶して基地の強度を向上
させるのに役立つため、更に強度を必要とする場合に添
加されるが、Ｎｉ が１−未満ではその効果が発揮され
ず、１０ｓを超えると基地が軟化し、耐摩耗性が低下す
るため、Ｎｉは１〜１０−とした。Ni (nickel) is solid dissolved in the Fe base and helps improve the strength of the base, so it is added when further strength is required, but if Ni is less than 1, the effect will not be exhibited, and after 10 s If the Ni content exceeds 1 to 10, the base becomes soft and the wear resistance decreases.
ｐｂ （鉛）の焼結合金への溶浸は、よシきびしい条
件下で使用されるバルブシートの場合に行われる。溶浸
されたｐｂは、パルプとバルブシートの接触部に介在し
てＰｂ酸化物層を形成することだより潤滑剤として作用
してパルプ及びバルブシート相互の耐摩耗性を向上させ
るが。Infiltration of sintered alloys with PB (lead) is carried out in the case of valve seats used under more severe conditions. The infiltrated Pb acts as a lubricant by forming a Pb oxide layer at the contact area between the pulp and the valve seat, thereby improving mutual wear resistance between the pulp and the valve seat.
Ｐｂ の溶浸が１−未満ではｐｂ溶浸の効果が発揮され
ず、２０チを超えて溶浸すると焼結合金のスケルトンが
弱化して摩耗が増大することから１〜２０チとした。If the infiltration of Pb is less than 1 inch, the effect of Pb infiltration will not be exhibited, and if the infiltration exceeds 20 inches, the skeleton of the sintered alloy will weaken and wear will increase.
（実施例）
以下に本発明を実施例により説明するがこれによシ本発
明は何ら限定されるものでない。(Examples) The present invention will be explained below with reference to Examples, but the present invention is not limited thereto in any way.
実施例１ ０２％、Ｃｒ３０％、Ｗｌｏ％、Ｎｂ５＊。Example 1 02%, Cr30%, Wlo%, Nb5*.
Ｆｅ ５〜及び残部がＣＯからなる合金アトマイズ粉
（％、００メツ７瓢）１５％、黒鉛粉末（−３５０）ｌ
７ ’／工） １．５１％ カルボ＝ｋＮｉ 粉末（
１０μｍ以下） ３チ及び残部アトマイズ鉄粉（％、０
０メツシエ）に潤滑剤としてステアリン酸亜鉛粉末α８
ｓとなる割合でこれらを混合した後、この混合粉末を金
型内に充填し、成形圧カフ Ｔｏｎ ／ ｃｙ／Ｉで成
形してバルブシート粗形状ｊ１ Ｍ±【） ；ｌメト
／ ｌｋ ａ獄 Ｉ Ｑ −ｗ ／ 〜」
＼ 、Ｐ−（ａ ４− ＞ Δ１粉末成形体を
アンモニア分解ガス雰囲気中で１１５０℃の温度にて６
０分間焼結して、密度ＺＯＰ／ｃｒ／ｌの焼結体を得た
。得られた焼結体を排気弁座の形状に加工して排気量２
０００ｃｃ、４気筒のディーゼルエンジンに装着し、全
負荷で２００時間台上耐久試験を実施し、バルブシート
当り面幅増加量及びパルプ摩耗量を測定した。なお相手
パルプにはＪＩ８ ＮＦＣ７５１を用いた。Alloy atomized powder (%, 00 7 gourd) consisting of 5~Fe and the balance CO 15%, graphite powder (-350) l
7'/engine) 1.51% Carbo=kNi powder (
10 μm or less) 3 pieces and the rest atomized iron powder (%, 0
Zinc stearate powder α8 as a lubricant for
After mixing these at a ratio of s, this mixed powder is filled into a mold and molded with a molding pressure cuff of Ton / cy / I to obtain a rough valve seat shape j1 M±[);
/ lka prison IQ-w / ~”
\, P-(a4->Δ1) The powder compact was heated at a temperature of 1150°C in an ammonia decomposition gas atmosphere.
Sintering was performed for 0 minutes to obtain a sintered body having a density of ZOP/cr/l. The obtained sintered body is processed into the shape of an exhaust valve seat and the displacement is 2.
000cc, 4-cylinder diesel engine, a bench durability test was conducted for 200 hours at full load, and the amount of increase in face width per valve seat and the amount of pulp wear were measured. Note that JI8 NFC751 was used as the partner pulp.
実施例２−８
各材料の組成を次表に示す各組成割合に変更したほかは
実施例１と同様に行なって各焼結体を得た。ただし実施
例５．４．７及び８は得られた焼結体をｐｂ塊と接触さ
せて再度アンモニア分解ガス中１０５０℃で３０分間加
熱して焼結体中にｐｂを溶浸したものである。得られた
各焼結体を弁座形状に加工し喪後実施例１と同様の試験
を行なった。Example 2-8 Each sintered body was obtained in the same manner as in Example 1 except that the composition of each material was changed to each composition ratio shown in the following table. However, in Examples 5.4.7 and 8, the obtained sintered body was brought into contact with the PB lump and heated again at 1050°C for 30 minutes in ammonia decomposition gas to infiltrate the PB into the sintered body. . Each of the obtained sintered bodies was processed into a valve seat shape, and the same tests as in Example 1 were conducted after the molding.
比較例１及び２
本発明焼結体の代わりに比較例１としてＪＩＳＦＣ！５
０鋳鉄、比紳例２としてＪＩＳ耐、Ｉ５Ａ鋼材Ｓ開４Ｂ
を用いて弁座形状に加工し、これらを実施例１と同様に
試験してバルブシート当り面幅増加量及びパルプ摩耗量
を測定した。Comparative Examples 1 and 2 JISFC! Comparative Example 1 instead of the sintered body of the present invention! 5
0 cast iron, JIS resistance as ratio 2, I5A steel S open 4B
These were processed into the shape of a valve seat, and tested in the same manner as in Example 1 to measure the amount of increase in surface width per valve seat and the amount of pulp wear.
以上の測定結果をまとめて次表に示す。The above measurement results are summarized in the following table.
表かられかるように実施例１〜８のバルブシート当り面
幅増加量はｃｌ、１〜（Ｌ２龍で、比較例１及び２の１
．２及び１．４０に比してかなシ小さな値を示しており
、実施例１〜８の焼結合金は過酷な条件下で使用される
ディーゼルエンジンの弁座材料としても耐摩耗性に優れ
ていることがわかる。また実施例１〜８のバルブ摩耗量
は３ないしＢ ｐｍで比較例１及び２の５０及び４０ｐ
ｍに比してかなり小さく、実施例１〜８の焼結合金は相
手材であるパルプに対する攻撃性が低い。As can be seen from the table, the amount of increase in surface width per valve seat in Examples 1 to 8 was cl, 1 to (L2 dragon, 1 in Comparative Examples 1 and 2)
．． 2 and 1.40, and the sintered alloys of Examples 1 to 8 have excellent wear resistance as valve seat materials for diesel engines used under harsh conditions. I know that there is. Further, the valve wear amount of Examples 1 to 8 was 3 to B pm, and the amount of valve wear of Comparative Examples 1 and 2 was 50 and 40 Pm.
It is considerably smaller than m, and the sintered alloys of Examples 1 to 8 have low aggressiveness against pulp, which is the mating material.
（発明の効果）
本発明のバルブシート用鉄系焼結合金は上記したように
合金粒子分パーライトを主体とする鉄基地中に均一に分
散させたので耐摩耗性に優れ、かつ相手材であるパルプ
に対する攻撃性が低く、バルブシート用焼結合金として
最適なものである。(Effects of the Invention) As mentioned above, the iron-based sintered alloy for valve seats of the present invention has excellent wear resistance because the alloy particles are uniformly dispersed in the iron base mainly composed of pearlite, and it is compatible with the mating material. It has low aggressiveness against pulp and is ideal as a sintered alloy for valve seats.
Claims (4)
ステン（Ｗ）５〜２０％、バナジウム（Ｖ）又はニオブ
（Ｎｂ）の１種又は２種２〜２０％、鉄（Ｆｅ）２０％
以下、炭素（Ｃ）０．５〜３％及び残部コバルト（Ｃｏ
）からなる合金粒子５〜２５％を、炭素（Ｃ）０．５〜
２％及び残部鉄（Ｆｅ）と不可避不純物からなるパーラ
イトを主体とする基地中に均一に分散させたことを特徴
とするバルブシート用鉄系焼結合金。(1) By weight, chromium (Cr) 10-70%, tungsten (W) 5-20%, one or both of vanadium (V) or niobium (Nb) 2-20%, iron (Fe) 20% %
Below, carbon (C) 0.5 to 3% and the balance cobalt (Co
), 5 to 25% of alloy particles consisting of 0.5 to 25% of carbon (C)
An iron-based sintered alloy for valve seats, characterized in that it is uniformly dispersed in a matrix mainly composed of pearlite, which is composed of 2% iron (Fe) and inevitable impurities.
ステン（Ｗ）５〜２０％、バナジウム（Ｖ）又はニオブ
（Ｎｂ）の１種又は２種２〜２０％、鉄（Ｆｅ）２０％
以下、炭素（Ｃ）０．５〜３％及び残部コバルト（Ｃｏ
）からなる合金粒子５〜２５％を、炭素（Ｃ）０．５〜
２％、ニッケル（Ｎｉ）１〜１０％及び残部鉄（Ｆｅ）
と不可避不純物からなるパーライトを主体とする基地中
に均一に分散させたことを特徴とするバルブシート用鉄
系焼結合金。(2) By weight, chromium (Cr) 10-70%, tungsten (W) 5-20%, one or both of vanadium (V) or niobium (Nb) 2-20%, iron (Fe) 20% %
Below, carbon (C) 0.5 to 3% and the balance cobalt (Co
), 5 to 25% of alloy particles consisting of 0.5 to 25% of carbon (C)
2%, nickel (Ni) 1-10% and balance iron (Fe)
An iron-based sintered alloy for valve seats, which is characterized by being uniformly dispersed in a base mainly consisting of pearlite and inevitable impurities.
テン（Ｗ）５〜２０％、バナジウム（Ｖ）又はニオブ（
Ｎｂ）の１種又は２種２〜２０％、鉄（Ｆｅ）２０％以
下、炭素（Ｃ）０．５〜３％及び残部コバルト（Ｃｏ）
からなる合金粒子５〜２５％を、炭素（Ｃ）０．５〜２
％、及び残部鉄（Ｆｅ）と不可避不純物からなるパーラ
イトを主体とする基地中に均一に分散してなる焼結合金
に鉛（Ｐｂ）１〜２０％を溶浸したことを特徴とするバ
ルブシート用鉄系焼結合金。(3) Chromium (Cr) 10-70%, tungsten (W) 5-20%, vanadium (V) or niobium (by weight)
2 to 20% of one or two types of Nb), 20% or less of iron (Fe), 0.5 to 3% of carbon (C), and the balance cobalt (Co)
5 to 25% of alloy particles consisting of carbon (C) 0.5 to 2
A valve seat characterized by infiltrating 1 to 20% of lead (Pb) into a sintered alloy that is uniformly dispersed in a pearlite-based matrix consisting of 1.5% and the balance iron (Fe) and unavoidable impurities. Iron-based sintered alloy.
テン（Ｗ）５〜２０％、バナジウム（Ｖ）又はニオブ（
Ｎｂ）の１種又は２種２〜２０％、鉄（Ｆｅ）２０％以
下、炭素（Ｃ）０．５〜３％及び残部コバルト（Ｃｏ）
からなる合金粒子５〜２５％を、炭素（Ｃ）０．５〜２
％、ニッケル（Ｎｉ）１〜１０％及び残部鉄（Ｆｅ）と
不可避不純物からなるパーライトを主体とする基地中に
均一に分散してなる焼結合金に鉛（Ｐｂ）１〜２０％を
溶浸したことを特徴とするバルブシート用鉄系焼結合金
。(4) Chromium (Cr) 10-70%, tungsten (W) 5-20%, vanadium (V) or niobium (by weight)
2 to 20% of one or two types of Nb), 20% or less of iron (Fe), 0.5 to 3% of carbon (C), and the balance cobalt (Co)
5 to 25% of alloy particles consisting of carbon (C) 0.5 to 2
%, 1 to 10% of nickel (Ni) and 1 to 20% of lead (Pb) are infiltrated into a sintered alloy that is uniformly dispersed in a pearlite-based matrix consisting of 1 to 10% of nickel (Ni) and the balance iron (Fe) and inevitable impurities. A ferrous sintered alloy for valve seats that is characterized by:
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60-223282 | 1985-10-07 | ||
| JP22328285 | 1985-10-07 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62188758A true JPS62188758A (en) | 1987-08-18 |
Family
ID=16795684
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23073186A Pending JPS62188758A (en) | 1985-10-07 | 1986-09-29 | Ferrous sintered alloy for valve seat |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62188758A (en) |
-
1986
- 1986-09-29 JP JP23073186A patent/JPS62188758A/en active Pending
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