JPS6164855A - Iron compound sintered alloy for valve seat - Google Patents
Iron compound sintered alloy for valve seatInfo
- Publication number
- JPS6164855A JPS6164855A JP18409984A JP18409984A JPS6164855A JP S6164855 A JPS6164855 A JP S6164855A JP 18409984 A JP18409984 A JP 18409984A JP 18409984 A JP18409984 A JP 18409984A JP S6164855 A JPS6164855 A JP S6164855A
- Authority
- JP
- Japan
- Prior art keywords
- iron
- sintering
- alloy
- sintered alloy
- powder
- 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
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
内燃機関用バルブシート、特に自動車用内燃機関のバル
ブシートには、ガンリン燃料の無鉛化によるパルブリセ
ツション防止のため種々の材料が提案されている。例え
ばFeMo、 Co、 Cを含有する耐摩耗性の良好な
鉄系焼結合金等が挙げられる。[Detailed Description of the Invention] [Field of Industrial Application] Various materials have been proposed for valve seats for internal combustion engines, particularly for valve seats for automobile internal combustion engines, in order to prevent pulse reset due to the use of lead-free Ganlin fuel. ing. Examples include iron-based sintered alloys containing FeMo, Co, and C and having good wear resistance.
しかしながら、近年、内燃機関に対する高性能化の要求
からバルブシートに対する要求もきびしくなり、耐熱性
、耐食性、耐摩耗性等のより以上の改善が望まれている
。これらの要望を解決するために高価な材料を大量に使
用することが考えられるがコスト高になる。However, in recent years, demands on valve seats have become stricter due to demands for higher performance in internal combustion engines, and further improvements in heat resistance, corrosion resistance, abrasion resistance, etc. are desired. In order to meet these demands, it is conceivable to use a large amount of expensive materials, but this will result in high costs.
本発明は耐熱性、耐食性、耐摩耗性等に優れたバルブシ
ート用鉄系焼結合金を提供することを目的とするもので
ある。An object of the present invention is to provide an iron-based sintered alloy for valve seats that has excellent heat resistance, corrosion resistance, wear resistance, etc.
本発明のバルブシート用鉄系焼結合金は、a)、Feを
素地とし、
全重量比で、
b)、Cα3〜2%、
C)\Co 5〜15%、
d)、Moを60〜70重量%含有するFeMo 5〜
15%、及び
e)、焼結後Cr、 Mo、 W及びVからなる群から
選ばれる元素1種又は2種以上を晶出又は析出する硬さ
Hv 800〜1800の炭化物を含有するCr、 M
o、 W、 Co及びSiのうちの1種又は2種以上5
〜40重量%、Ca、S〜2重量%及び残部不可避的不
純物を含有するFeからなる焼結後の硬さがHv 30
0〜900となる鉄基合金の1種又は2種以上3〜20
%
とからなシ、FeMo及び鉄基合金が焼結合金中に均一
に分散していることを特徴とする。The iron-based sintered alloy for valve seats of the present invention has a) Fe as a base material, b) Cα 3-2%, C) \Co 5-15%, d) Mo 60-60%. FeMo containing 70% by weight 5~
15%, and e) Cr, M containing a carbide with a hardness Hv of 800 to 1800 that crystallizes or precipitates one or more elements selected from the group consisting of Cr, Mo, W, and V after sintering.
One or more of o, W, Co, and Si5
The hardness after sintering is Hv 30, consisting of Fe containing ~40% by weight, Ca, ~2% by weight S, and the remainder unavoidable impurities.
One or more types of iron-based alloys having a value of 0 to 900, 3 to 20
%, FeMo, and iron-based alloy are uniformly dispersed in the sintered alloy.
以下、本発明においてチは特記しない限り、重量%を示
す。Hereinafter, in the present invention, unless otherwise specified, CH indicates weight %.
本発明において、鉄基合金として、Moα5〜6チ、C
r6〜18%、V (L 1〜1 %、Si [11〜
1%、Cα5〜2%及び残部不可避的不純物を含有する
Feからなる鉄基合金、Mo 1〜10%、Cr1〜1
0 %、■15〜6チ、Siα1〜1%、W1〜10%
、C0,5〜2%及び残部不可避的不純物を含有するF
eからなる鉄基合金、Mo15〜6%、Crα5〜6%
、Vα5〜6%、Siα1〜1チ、W 5〜15 ’i
r、 Co 5〜15%、Cα5〜2%及び残部不可避
的不純物を含有するFeからなる鉄基合金のうち少なく
とも1種を用いることが好ましい。In the present invention, as the iron-based alloy, Moα5-6CH, C
r6~18%, V(L1~1%, Si[11~
Iron-based alloy consisting of Fe containing 1%, Ca 5-2% and the balance unavoidable impurities, Mo 1-10%, Cr 1-1
0%, ■15~6chi, Siα1~1%, W1~10%
, C0.5-2% and the remainder containing unavoidable impurities
Iron-based alloy consisting of e, Mo15-6%, Crα5-6%
, Vα5-6%, Siα1-1ch, W 5-15'i
It is preferable to use at least one type of iron-based alloy consisting of Fe containing 5 to 15% of Co, 5 to 2% of Ca, and the remainder unavoidable impurities.
また、必要によシ、上記の焼結合金にPbを1〜20チ
溶浸することも好ましい。Furthermore, if necessary, it is also preferable to infiltrate 1 to 20 pieces of Pb into the above sintered alloy.
以下、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 below.
C(炭素)は、焼結時に鉄素地中に固溶、拡散し、焼結
を促進し、鉄素地の強化を計るだめのもので、α3チ未
満のCの添加ではその効果が見られず、2%を越えて添
加すると、Cが遊離黒鉛として素地中に残留する量が多
くなりすぎて素地の強度がかえって低下することから、
13〜2%と限定した。C (carbon) is a solid solution and diffuses into the iron base during sintering, promotes sintering, and strengthens the iron base, and the addition of C less than α3 has no effect. If it is added in excess of 2%, the amount of C remaining in the matrix as free graphite becomes too large and the strength of the matrix decreases.
It was limited to 13-2%.
Co tコバルト)は焼結時に鉄素地中に固溶してこれ
を強化し、耐熱性の向上と高温強度を維持する効果があ
るが、3%未満のCOの添加ではその効果がみられず、
一方COを15チを越えて添加してもそれ以上の添加効
果は得られず、逆に素地が軟化して摩耗が増加し、また
COは高価なためCoを大量に添加することは経済的に
不利であることから3〜15チと限定した。Co (cobalt) dissolves into the iron base during sintering and strengthens it, improving heat resistance and maintaining high-temperature strength, but this effect is not seen when less than 3% of CO is added. ,
On the other hand, even if more than 15 inches of CO is added, no further effect will be obtained; on the contrary, the substrate will become softer and wear will increase, and since CO is expensive, it is not economical to add a large amount of Co. The number was limited to 3 to 15 inches because it was disadvantageous.
FeMo (フェロモリブデン)は、Moを60〜70
%含有した場合、ビッカース硬さHv600〜1300
の硬さを有しており、素地中にFeMoの微細な硬質粒
子を分散させ、その敷石効果に工って耐摩耗性を発揮さ
せるもので、FeMoの添加が3%未満では耐摩耗成分
が少なすぎて耐摩耗性の効果が表われず、一方15%を
越えてFeMoを添加すると耐摩耗成分が多くなりすぎ
て相手の部材を損傷させ、また切削加工を困難にするこ
とから、3〜15%と限定した。FeMo (ferromolybdenum) has Mo of 60 to 70
%, Vickers hardness Hv600-1300
It has a hardness of If it is too small, the effect of wear resistance will not be exhibited, and on the other hand, if FeMo is added in excess of 15%, the wear-resistant component will be too large, damaging the mating member and making cutting difficult. It was limited to 15%.
鉄基合金は、鉄素地中に一部拡散して素地の強化と耐熱
性を高めるとともに、微細に分散する炭化物により耐摩
耗性を発揮するもので、鉄基合金の添加が3%未満では
上記効果が少なく、一方20%を越えて添加すると逆に
素地の強度が低下する。Iron-based alloys partially diffuse into the iron base to strengthen the base and increase heat resistance, and exhibit wear resistance due to finely dispersed carbides.If the addition of iron-based alloys is less than 3%, the above-mentioned It has little effect, and on the other hand, if it is added in excess of 20%, the strength of the base material decreases.
PbO溶浸は更にきびしい使用条件の場合に行い、Pb
がバルブとバルブシートとの接触部に介在し、Pb酸化
物層を形成することによシ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もので、
pb溶浸が1%未満ではPb溶浸の効果が表われず、2
0%を越えるpb溶浸では、焼結体のスケルトンが弱化
して、摩耗が増大することから1〜20%と限定した。PbO infiltration is performed under more severe usage conditions, and
is present at the contact area between the valve and the valve seat, and acts as a lubricant by forming a Pb oxide layer to improve mutual wear resistance between the pulp and the valve seat.
If the Pb infiltration is less than 1%, the effect of Pb infiltration will not appear;
Pb infiltration exceeding 0% weakens the skeleton of the sintered body and increases wear, so it was limited to 1 to 20%.
焼結体を製造するための混合粉末を成形する際の成形圧
は6〜7 t/−がよい。The compacting pressure when compacting the mixed powder for producing a sintered body is preferably 6 to 7 t/-.
また、成形体の焼結は還元性雰囲気中で1,100〜1
,250℃の温度にて30〜60分間加熱処理するとよ
い。Pbを溶浸する場合、該焼結体をpbと接触させて
、再度、還元性雰囲気中で1.000〜1.100℃の
温度にて30〜60分間加熱処理するとよい。In addition, the sintering of the molded body is performed in a reducing atmosphere with a
, 250° C. for 30 to 60 minutes. When Pb is infiltrated, the sintered body is preferably brought into contact with Pb and heat-treated again at a temperature of 1.000 to 1.100° C. for 30 to 60 minutes in a reducing atmosphere.
本発明において、炭素α6〜2%の添加は、素地を強化
し、Co 3〜15%のざミ加は耐熱性の維持に効果を
示し、Moを60〜70%含有するFeMo 3〜15
%の添加は摩耗性を向上書せ、更に焼結後Cr、 Mo
、 W、 Vのうちの1株又は2種以上の晶出又は析出
するビッカース硬さHv 800〜1800の炭化物を
有するCr・Mo・W・V・Co・Siのうちの1種又
は2株以上5〜40%、Cα5〜2%及び残部不可避的
不純物を含有するFeからなる焼結後の硬さがHv50
0〜900となる鉄基合金の1種又Fi23i以上3〜
20%の添加は素地を強化し、耐熱性及び耐摩耗性を向
上させるように作用する。また必要によりPbを1〜2
0%溶浸することは耐摩耗性及び潤滑性を向上させるこ
とができる。In the present invention, the addition of 6 to 2% carbon α strengthens the substrate, the roughening of 3 to 15% Co is effective in maintaining heat resistance, and the addition of FeMo 3 to 15 containing 60 to 70% Mo
The addition of Cr, Mo
, W, V, one or more strains of Cr, Mo, W, V, Co, Si having a carbide with a Vickers hardness of Hv 800 to 1800 that crystallizes or precipitates. Hardness after sintering is Hv50, consisting of Fe containing 5-40%, Cα5-2%, and the remainder unavoidable impurities.
One of the iron-based alloys having a value of 0 to 900 or Fi23i or more of 3 to 900
The 20% addition acts to strengthen the matrix and improve heat and abrasion resistance. Also, if necessary, add 1 to 2 Pb.
0% infiltration can improve wear resistance and lubricity.
以下、本発明を実施例によシ説明する。 The present invention will be explained below using examples.
実施例
Fe粉末(−100メツシユ)、FeMo粉末(−20
0メソシユ)、Co粉末(−100メッシ、)、C粉末
(−325メツシユ)及び表1に示す鉄基合金粉末(−
100メツシユ)を表2に示す組成により配合し、更に
ステアリン酸亜鉛−1(15〜1チ加え、混合し、成形
圧7t々で成形して成形体を作製する。次いでこの成形
体をアンモニア分解ガス雰囲気中で1.150℃の温度
にて45分間焼結を行った。Example Fe powder (-100 mesh), FeMo powder (-20 mesh)
0 mesh), Co powder (-100 mesh), C powder (-325 mesh), and iron-based alloy powder shown in Table 1 (-
100 mesh) according to the composition shown in Table 2, further add 15 to 1 piece of zinc stearate, mix, and mold at a molding pressure of 7 tons to produce a molded body.Then, this molded body is decomposed with ammonia. Sintering was carried out at a temperature of 1.150° C. for 45 minutes in a gas atmosphere.
また、試料番号6.7及び10は得られた焼結体をアン
モニア分解ガス雰囲気中でPb塊とともに再度1.05
0℃の温度にて30分間加熱してpbの溶浸を行った。In addition, for sample numbers 6.7 and 10, the obtained sintered bodies were re-coupled with Pb lumps in an ammonia decomposition gas atmosphere.
Pb was infiltrated by heating at a temperature of 0° C. for 30 minutes.
特開昭48−90907号公報に記載されているバルブ
シートを比較材とした、
これらの各材料の摩耗量、圧環強さ、全体硬さ及び鉄基
合金の硬さを測定し、結果を表3に示す。瓜耗量の測定
は、第1図に示すように試験片1を545C焼入れ焼も
どし材製のa−夕2に押し付けばね3で押し付け、ロー
タ2を回転させ、すべり速度(15m/sec 、 摩
耗距離100m。Using the valve seat described in JP-A No. 48-90907 as a comparison material, the wear amount, radial crushing strength, overall hardness, and hardness of the iron-based alloy of each of these materials were measured, and the results are presented. Shown in 3. To measure the wear amount, as shown in Fig. 1, the test piece 1 was pressed against the a-plate 2 made of 545C quenched and tempered material with a spring 3, the rotor 2 was rotated, and the sliding speed (15 m/sec, abrasion) was measured. Distance: 100m.
最終荷重2.1 KPの条件で行い、第2図に示す工う
に試験片1の摩擦幅4と摩耗量とした。The test was carried out under the conditions of a final load of 2.1 KP, and the friction width 4 and the wear amount of the test piece 1 shown in FIG. 2 were set.
表1 鉄基合金組成
表2 実施例組成
表3 実施例結果
表3に示した結果かられかるように、FeMo、Co、
Cの組成がそれぞれ5,5,1.0%である発明材の摩
耗量は1.81〜1.93mでそれに相当する比較材の
2.00諒よシ小さく、またFeN1o * Co *
Cの組成がそれぞれ10.10.1.0%である発明材
の摩耗iは1.65及び1.70!IImでそれに相当
する比較材の1.77閣よシ小さく、発明材は耐摩性に
優れていた。また、Pbtl−溶浸し友発明材の耐摩耗
性は比較材と同じPbの溶浸率では比較材ニジ優れ七お
り、Pbの溶浸率が低い場合でも溶浸していないものよ
シ優れていた。Table 1 Iron-based alloy composition table 2 Example composition table 3 Example results As can be seen from the results shown in Table 3, FeMo, Co,
The wear amount of the invented materials with C compositions of 5, 5, and 1.0%, respectively, was 1.81 to 1.93 m, which was 2.00 m smaller than that of the corresponding comparative material, and FeN1o * Co *
The wear i of the invented materials with C compositions of 10, 10, and 1.0%, respectively, is 1.65 and 1.70! IIm was 1.77 mm smaller than the corresponding comparative material, and the invented material had excellent wear resistance. In addition, the wear resistance of the Pbtl-infiltrated material was superior to that of the comparative material at the same Pb infiltration rate as the comparative material, and was superior to that of the non-infiltrated material even when the Pb infiltration rate was low. .
発明材の圧環強さは比較材と同程度のものもあるが、成
分組成によっては比較材よりかなり大きな値を示し、優
れていた。The radial crushing strength of the invented materials was comparable to that of the comparative materials in some cases, but depending on the component composition, the radial crushing strength of the invented materials was significantly higher than that of the comparative materials.
本発明は、上記したような成分組成とすることによシ優
れた耐熱性、耐食性及び耐摩耗性のバルブシート用鉄系
焼結合金を得ることができる。The present invention makes it possible to obtain an iron-based sintered alloy for valve seats that has excellent heat resistance, corrosion resistance, and wear resistance by having the above-mentioned component composition.
更に成分組成を調節することにより従来のバルブシート
よりかなり優れた圧環強さのバルブシートも得ることが
できる。Furthermore, by adjusting the component composition, a valve seat with considerably superior radial crushing strength than conventional valve seats can be obtained.
更に、Co、Moのような高価な材量を大量に使用しな
くても本発明の鉄基合金を用いることに工り、優れた耐
摩耗性のバルブシートを得ることができる。Further, by using the iron-based alloy of the present invention, a valve seat with excellent wear resistance can be obtained without using large quantities of expensive materials such as Co and Mo.
第1図は本発明の一実施例で行った摩耗試験を示す模式
図、
第2図は第1図の試験片の摩耗量を示す図を表わす。
図中、
1・・・試験片 2・・・ロータ3・・・押
し付けばね 4・・・摩耗幅特許出願人 トヨ
タ自動車株式会社同 日本粉末合金株式会社
代理人 弁理士 萼 優 美 ほか1名才1図
1・−詰、駿方
2・・・ロータ
3・・・1甲しイ寸けtarね
牙2図FIG. 1 is a schematic diagram showing a wear test conducted in an embodiment of the present invention, and FIG. 2 is a diagram showing the amount of wear of the test piece shown in FIG. 1. In the figure, 1... Test piece 2... Rotor 3... Pressing spring 4... Wear width Patent applicant: Toyota Motor Corporation, Japan Powder Alloy Co., Ltd., agent, patent attorney, Yumi Kaede, and one other person 1 Figure 1 - Tsume, Shunkata 2... Rotor 3... 1 Insert size, Tar, Fang 2 Figure
Claims (2)
5%、及び e)、焼結後Cr、Mo、W及びVからなる群から選ば
れる元素1種又は2種以上を晶出 又は析出する硬さHv800〜1800の炭化物を含有
するCr、Mo、W、Co及びSiのうちの1種又は2
種以上5〜40重量%、 C0.5〜2重量%及び残部不可避的不純 物を含有するFeからなる焼結後の硬さが Hv300〜900となる鉄基合金の1種又は2種以上
3〜20% とからなり、FeMo及び鉄基合金が焼結合金中に均一
に分散していることを特徴とするバルブシート用鉄系焼
結合金。(1) FeMo3-1 which is made of Fe as a base material and contains b), C0.3-2%, c), Co3-15%, d), Mo 60-70% by weight in total weight ratio.
5%, and e) Cr, Mo, containing a carbide with a hardness of Hv 800 to 1800 that crystallizes or precipitates one or more elements selected from the group consisting of Cr, Mo, W and V after sintering. One or two of W, Co and Si
One or more iron-based alloys having a hardness after sintering of 300 to 900 Hv, consisting of Fe containing 5 to 40% by weight of seeds, 0.5 to 2% of C, and the remainder unavoidable impurities. An iron-based sintered alloy for valve seats, characterized in that FeMo and an iron-based alloy are uniformly dispersed in the sintered alloy.
5%、及び e)、焼結後Cr、Mo、W及びVからなる群から選ば
れる元素1種又は2種以上を晶出 又は析出する硬さHv800〜1800の炭化物を含有
するCr、Mo、W、Co及びSiのうちの1種又は2
種以上5〜40重量 %、C0.5〜2重量%及び残部不可避的 不純物を含有するFeからなる焼結後の硬 さがHv300〜900となる鉄基合金の1種又は2種
以上3〜20% とからなり、FeMo及び鉄基合金が焼結合金中に均一
に分散してなる焼結合金にPbを1〜20重量%溶浸せ
しめたことを特徴とするバルブシート用鉄系焼結合金。(2) a), FeMo3-1 which is made of Fe and contains b), C0.3-2%, c), Co3-15%, and d), Mo 60-70% by weight in total weight ratio.
5%, and e) Cr, Mo, containing a carbide with a hardness of Hv 800 to 1800 that crystallizes or precipitates one or more elements selected from the group consisting of Cr, Mo, W and V after sintering. One or two of W, Co and Si
One or two or more iron-based alloys having a hardness after sintering of 300 to 900 Hv, consisting of Fe containing 5 to 40% by weight of seeds, 0.5 to 2% by weight of C, and the balance unavoidable impurities. An iron-based sintered alloy for a valve seat, characterized in that the sintered alloy is made of a sintered alloy in which FeMo and an iron-based alloy are uniformly dispersed in the sintered alloy, and is infiltrated with 1 to 20% by weight of Pb. Money.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18409984A JPS6164855A (en) | 1984-09-03 | 1984-09-03 | Iron compound sintered alloy for valve seat |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18409984A JPS6164855A (en) | 1984-09-03 | 1984-09-03 | Iron compound sintered alloy for valve seat |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS6164855A true JPS6164855A (en) | 1986-04-03 |
Family
ID=16147372
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP18409984A Pending JPS6164855A (en) | 1984-09-03 | 1984-09-03 | Iron compound sintered alloy for valve seat |
Country Status (1)
Country | Link |
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JP (1) | JPS6164855A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS63317646A (en) * | 1987-06-19 | 1988-12-26 | Mitsubishi Metal Corp | Fe based sintered alloy having excellent sliding characteristic |
JPH01201439A (en) * | 1988-02-05 | 1989-08-14 | Nissan Motor Co Ltd | Heat-resistant and wear-resistant iron-based sintered alloy |
JPH01268849A (en) * | 1988-04-18 | 1989-10-26 | Riken Corp | Wear-resistant iron-base sintered alloy and its production |
US6726517B2 (en) | 2000-11-20 | 2004-04-27 | Matsushita Electric Industrial Co., Ltd. | Cold cathode forming process |
-
1984
- 1984-09-03 JP JP18409984A patent/JPS6164855A/en active Pending
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS63317646A (en) * | 1987-06-19 | 1988-12-26 | Mitsubishi Metal Corp | Fe based sintered alloy having excellent sliding characteristic |
JPH01201439A (en) * | 1988-02-05 | 1989-08-14 | Nissan Motor Co Ltd | Heat-resistant and wear-resistant iron-based sintered alloy |
JPH01268849A (en) * | 1988-04-18 | 1989-10-26 | Riken Corp | Wear-resistant iron-base sintered alloy and its production |
US5080713A (en) * | 1988-04-18 | 1992-01-14 | Kabushiki Kaisha Riken | Hard alloy particle dispersion type wear resisting sintered ferro alloy and method of forming the same |
US6726517B2 (en) | 2000-11-20 | 2004-04-27 | Matsushita Electric Industrial Co., Ltd. | Cold cathode forming process |
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