JPS6050151A - Fe-base sintered material for sliding member of internal-combustion engine - Google Patents
Fe-base sintered material for sliding member of internal-combustion engineInfo
- Publication number
- JPS6050151A JPS6050151A JP15730983A JP15730983A JPS6050151A JP S6050151 A JPS6050151 A JP S6050151A JP 15730983 A JP15730983 A JP 15730983A JP 15730983 A JP15730983 A JP 15730983A JP S6050151 A JPS6050151 A JP S6050151A
- Authority
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- Japan
- Prior art keywords
- ratio
- mainly
- hard phase
- hardened
- density ratio
- Prior art date
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- Valve-Gear Or Valve Arrangements (AREA)
Abstract
Description
【発明の詳細な説明】
この発明は、すぐれた+lIiIM粍恰および耐スカッ
フィング性をイー1’ L、かつ著しく低い相手攻4%
’a w:有1..7t、〒に使用条f/lが高温上
・よび高面I−r斗での使用となる+tq燃機関の摺動
部材とL−c使用するのに−JLJ番゛O基炉、結n旧
に関−1イ超)のである。[Detailed Description of the Invention] This invention provides excellent +lIiIM structure and scuffing resistance, and extremely low opponent attack of 4%.
'a w: Yes 1. .. 7t, 〒The service condition f/l is used at high temperature and high surface I-r.+tq When used with the sliding member of the combustion engine and L-c. This is the old version.
ゲ来、内燃機関のロッカーアーム摺動面に用いらt]〜
るバント月、カッ3.バルブガイド、あるh(σ1−ス
リー プなとの摺動部材の製造に1小々の11′e基焼
結イ」イ:1が用いられている4、
一方、近年、例しば31j両の高速化、高効率化。Since then, it has been used for the rocker arm sliding surface of internal combustion engines]
Bant moon, Kak3. A small amount of 11'e-based sintered A:1 is used in the manufacture of sliding parts for valve guides, such as h(σ1-sleep).4 On the other hand, in recent years, for example, 31j Faster and more efficient.
および高出力化(、′こ伴い、と2t′1−ら内燃(晟
関の摺動7′1]3イメに対する使用条f’4= (d
、一段と厳L7さを増(7ており、これに対応するFe
基焼結材イ、)として(油I摩柱・til−を向トさせ
たものが持案さt’していZ)。and high output (,', 2t'1- et al. internal combustion (sliding of the gate 7'1) 3 image usage conditions f'4 = (d
, the severity of L7 has been further increased (7), and the corresponding Fe
As the base sintered material (a) (a material on which oil was applied) was used.
しか(〜、この上うな11Iil摩耗性Fe基焼結刊渭
1に1・・いては、そ牙]2自身のI紺摩耗fトは改善
されるよう(・ζなるものの、反面スヵノノイング発生
の問題や、相手攻撃性の一段の増大を避けることができ
ないのが現状である。However, it seems that the wear of the 2 itself is improved (・ζ, but on the other hand, the occurrence of scannoing is The current situation is that it is impossible to avoid problems and a further increase in the aggressiveness of the opponent.
そこ、で、本発明者等は、ト述のような観点から、1)
]j摩、I’l’、(イI::、1.t’ l−び:へ
1(ス1ノノフて/グ+1−に−4−ぐれるが、((1
丁 1(“1腎 i4.: jV (It (1)h−
s 占(風裏 糸占 1+、4 卓−15〜 1()
へ く イ1)1 究 イ←・ ♀−jプト壬)介活1
1犀−1重「11へ−Q (、i゛)、F A11l
lj!に関1゛る係は中111循を・う■、す)、
(:r 、’ Q、 5 =−8係、
(−! 2〜5 係、
1” : 0.0 2〜5 係、
l・Ao : (1,(l ii 〜 :3 係、↑〜
4r+:0.05 ヘー :3 %、CLIおJ二び!
’−(1’lのうちのl ’f、qオプこは2Tl(1
i’、 5−20循、全a−何し、さ0に嵌装((T:
i、i=、、しで、■、″1°j、、Zr、ト1(’
、lっ・よびN i)の91)の1種丑/こd21Φ以
上 ([02−s係、
を−真イ[L7、残りがFeと不可避イ・純′吻がらブ
rる組成、q(7ぴに半とシ7.て−1・ルチン))・
11・勉・11.在る素地(この’hL 介C: +1
4−’ S rlの初品、および(:H−Sl+ ’@
金やC!u、 ’−5rl−、[i’o介金の共晶のう
ちの少くともいずれがか分散相を形1jl (、で存在
する)に、面積率で20〜6()係の主とし7て1v1
30型の炭化物および複炭化物からなる硬質相が微細に
、望−舟しくは1[)・〜5 Q 77mの平均粒径て
、均一に分散した焼入れA、たにJ5焼ノ\れ・焼戻し
、 #11. l織を有し7、かつ理論密度比全85幅
以上と[〜/こド0基焼結利料は、すぐ)′シた面1摩
粍[1と面1スカノフイ/グ件苓τ治するにもかかわら
ず、相手攻撃14I;は著しく低く、したかつて、この
FG基焼結利別を、高温および高面圧下での苛酷な条件
で使用される内燃機関の摺動部材の製造(′ζ用いた場
合(・で1ぐバ/こ14[能を・著しく艮1(+1に亘
って発揮するとイツ知ν、 ’f Huだのである。Therefore, the inventors of the present invention, from the viewpoints mentioned above, 1)
] j ma, I'l', (ii I::, 1.t'
Ding 1 (“1 kidney i4.: jV (It (1) h-
s Fortune Telling (Wind Ura Thread Fortune Telling 1+, 4 Table -15 ~ 1()
Go to Ku I1) 1 Study I←・♀−jpt壬)Caregiving 1
1 rhinoceros - 1 layer "11-Q (,i゛), F A11l
lj! The 1st section related to 1'' goes to the 111th round in middle school), (: r,' Q, 5 = -8 section, (-! 2 to 5 section, 1": 0.0 2 to 5 section, l・Ao: (1, (l ii ~: 3 section, ↑~
4r+: 0.05 Hey: 3%, CLI OJ two!
'-(l 'f of 1'l, q opko is 2Tl(1
i', 5-20th cycle, all a-what, inserted into sa0 ((T:
i, i=,,shide,■,″1°j,,Zr,to1('
, l, and Ni) of 91), one kind of ox/ko d21Φ or more ([02-s section, wo-true [L7, the remainder is Fe and unavoidable A-pure' proboscis-like composition, q (7 Pinihan and Shi7. Te-1 Rutin))・
11・Tsutomu・11. The basis of existence (Kono'hL Intermediate C: +1
4-' S rl's first product, and (:H-Sl+ '@
Money and C! u, '-5rl-, [i'o At least one of the intermetallic eutectics has a dispersed phase in the form 1jl (exists in , ), with an area ratio of 20 to 6 ( ), and 7 Te1v1
Quenching A, J5 quenching and tempering in which the hard phase consisting of type 30 carbides and double carbides is finely dispersed, preferably with an average grain size of 1[). , #11. 1 weave 7, and the theoretical density ratio is 85 or more in width [~/Kodo 0 base sintering material is immediately)' Despite this, the FG-based sintering process has been extremely low, and this FG-based sintering process has been used in the manufacture of sliding parts for internal combustion engines that are used under harsh conditions at high temperatures and high surface pressures. When using ζ (・de1guba/ko14 [ability)・remarkably 艮1 (+1), it is wisdom ν, 'f Hu.
この発1叫は、」二記欠[1卯、(/l二もとついてな
されたものであつ−C1以下に成分組成、硬質相の面積
率、および理論密度比を上記の通り(で限定しまた理由
を一説明する33
Δ、 成づ〕組成
(a、) Cr
0シ成分には、素地Qrl′、!7I溶して、これ治二
強化せると共(/こ、C成分と結合(7て素地中に微、
4+11均一に分1)々する高硬吸の炭化物全形成1〜
、もってAA )T”lの耐19粍性を向」−させる作
用があるか、その含有量が05ダ未満では前記作用に所
望の効果がイ(Iら)7.ず、−力8・系を・1四ぐ−
こn゛有さぜると、相丁攻”$1’tか急激(f(二J
曽人ずもしうになることか0、その;)イイ量不二(1
13〜8%ど定めた。、
(b) (’
C成分(tこ姥1、メ・、!1j (、こ固7容し5−
C,とれ1・強化トるt’3か、(J 、1− 、 M
t)、さL−フに八’ 、 T]、、、 yir、
l(f、お、+、びN +)IJV分と結合して硬質相
の主要IJk分たる炭化物(複炭f1−物も含む)4丁
形成(−7、も−゛つで(1第1の面j佇糺4イ1’x
l#11−1−1させる作用かぁ)るが、そのλイ1
量が2係末/11jiJ″Cは前31暦′1・川して所
望の効果が得ら1シず、−・力5φな二、越えてつ1イ
1させると、炭化′1夕jの[flが多くなり・1き、
硬質、(11の割合がi7+i債率で60係を越えて高
くなつ〉て、相・丁攻撃怜−が著しく増大−Jるよつc
′(−なることから、そ−の含イ〕早!f:2〜5%と
定め/こ、1((・) P
P成分K i:i、す潤鈷萌に液([1不二グー、牛さ
」)−て焼結1イ16:向−十−させ、もって7(」オ
ーIを緻′i・;fシすると現、に、素を向上させる作
用があるが、その含イ」−匿が0.02係未満では前記
作用に所望の効果が得られず、一方5係を越えて含有さ
せると、制料の脆化が著しくなることから、その含有量
全002〜5%と定めた。This utterance was originally made based on ``2ki missing [1u, (/l2), and the component composition, the area ratio of the hard phase, and the theoretical density ratio were limited to below -C1 as described above ( Also, to explain the reason, 33 Δ, formed] composition (a,) The Cr0 component is dissolved in the base material Qrl', !7I to strengthen it and combine with the C component. (7) There is a small amount in the base material.
4+11 Uniform formation of carbide with high hardness 1)
7. If the content is less than 0.05 da, the desired effect is not achieved (I et al.) 7. zu, -force 8 system wo 14g-
If you have this, the partner attack"$1't or sudden(f(2J
Is it true that Sojinzu also becomes like that?
The rate was set at 13-8%. , (b) ('C component(tko姥1、me・、!1j
C, Tore 1/Reinforcement Toru t'3? (J, 1-, M
t), さL-fu ni 8', T],,, yir,
l (f, O, +, and N +) combine with the IJV component to form four carbides (including double carbon f1-) that are the main IJk component of the hard phase (-7, also -) (first 1 side j 4i 1'x
Is there an effect that causes l#11-1-1?), but that λi1
If the amount is 2/11jiJ''C, the desired effect cannot be obtained, and the force 5φ is exceeded, carbonization occurs. [fl becomes more and becomes 1,
Hard, (the ratio of 11 becomes higher than the 60th ratio at i7+i bond rate), and the attack rate increases significantly.
'(Since it becomes -, its inclusion A) Haya! f: 2 to 5% / Ko, 1 ((・) P P component K i: i, Sujun Kamoe liquid ([1 Fuji If you sinter 1-16: 1-16: direction, then 7('-I), it has the effect of improving the element, but its content is If the concentration is less than 0.02, the desired effect cannot be obtained, while if the content exceeds 5, the embrittlement of the material will become significant. %.
(d) M。(d) M.
MO酸成分は、上記のように炭化物全形成して、42別
の耐摩耗性を向−りさぜると共に、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0.05 e
!l)未満では前記作用に所望の効果が得られず、一方
3%を越えて含有させると、硬質相の割合が多くな9す
ぎて相手攻撃性が著しく増大するように力ることから、
その含有量’f 0.02〜;3飴と定めた。As mentioned above, the MO acid component completely forms carbides to improve the wear resistance of the base material, and also works to strengthen the base material by forming a solid solution therein. .05 e
! If the content is less than 1), the desired effect cannot be obtained, whereas if it is contained in excess of 3%, the proportion of the hard phase is too high, which significantly increases the aggressiveness of the opponent.
The content 'f 0.02 ~; 3 candy was determined.
(e) Mn
Mn成分には、MOとの共存において、素地に固溶して
、焼入性を向上さぜると共に、素地の靭性向上および強
化に寄与し、かつ複炭化物全形成して耐摩耗性全向上さ
せるほか、なじみ性を改善して相手攻撃性を緩和する作
用があるが、その含有量が0.05%未満では前記作用
に所望の効果が得られず、一方;3係を越えて含有させ
ると、焼入性向I−にJ:るノそ池の硬さ上層をきたし
、相手攻撃ttgが噌夫するJ、うに々ることから、そ
の含有−尾を0.05〜3係と定めた。(e) Mn The Mn component, when coexisting with MO, forms a solid solution in the base material, improves hardenability, contributes to improving and strengthening the toughness of the base material, and improves resistance by forming all double carbides. In addition to improving wear resistance, it has the effect of improving conformability and alleviating the aggressiveness of opponents, but if its content is less than 0.05%, the desired effect cannot be obtained; If the content exceeds J, the hardness of the hardening property I- will be higher than that of J:Runosoike, and the opponent's attack ttg will be distorted, so the content will be 0.05 to 3. The person in charge was appointed as the person in charge.
(’) CuおよびSn
これら両成分には、素地に固溶して、これ全強化するほ
か、CIIやSnの初晶、およびCu −Sn合金やC
1i −Sn −11’0合金の共晶のうちの少なくと
もいずれかからjl ZI I)) !f父粗相全形成
て素地中に存在し、この分散相の存在によって制料の熱
伝導性が向1ニするようになるので、摺動面の温度上昇
が抑制さね1、もって材PIの面jスカッフィング性が
向」−シ、さらに相手部拐とのなじみ性を確保し、イ目
手攻撃性を一段と抑制する作用があるが、その含有量、
が5飴未満でに、前記作用に所望の効果が得られず、一
方20チを越えて含有させても前記作用により−・層の
向上効果は現われないことから、軒済1牛を考慮して、
その含有量全5〜20係と定め/ヒ。(') Cu and Sn In addition to solid solution in the base material to fully strengthen it, Cu and Sn also contain primary crystals of CII and Sn, as well as Cu-Sn alloys and C
jl ZI I)) from at least one of the eutectics of the 1i-Sn-11'0 alloy! The presence of this dispersed phase improves the thermal conductivity of the material, suppressing the temperature rise of the sliding surface. It has the effect of improving scuffing properties, and also has the effect of ensuring compatibility with the opponent and further suppressing aggressiveness, but its content,
If the content is less than 5 candies, the desired effect cannot be obtained, and on the other hand, even if the content exceeds 20 candies, the effect of improving the layer will not appear due to the above action. hand,
Its content is determined to be between 5 and 20 in total.
(gI V 、Tj、、 Hf、 Zr、およびJvb
これらの成分には、OrおよびMo成分との共存におい
て、複炭化物を形成し、もって月別の耐摩耗性を一段と
向上させる作用があるので、特にすぐれた耐摩耗性が要
求される場合に必要に応じて含有されるが、その含有量
が0i係未満では所望の而」摩耗性向上効果が得られず
、一方5係を越えて含有させると、相手攻撃性が急激に
増大するようになることから、その含有量fi 0.1
〜5係と定めた。(gI V , Tj, , Hf, Zr, and Jvb
When these components coexist with Or and Mo components, they form double carbides, which have the effect of further improving monthly wear resistance, so they are necessary when particularly excellent wear resistance is required. However, if the content is less than 0i, the desired effect of improving wear resistance cannot be obtained, while if it is contained in more than 5, the aggressiveness of the opponent will increase rapidly. , its content fi 0.1
It was decided that it would be Section 5.
B、硬質相の面積率
この発明の飼料は、焼入れまたは焼入れ・焼戻し組織で
あるビッカース硬さで400以上の比較的高い硬さを有
するマルデンサイト全主体とした素地、およびこの素地
中に微細に、望ましくは10〜50μ7nの平均粒径で
、均一に分散し、主としてM2C型の炭化物および複炭
化物から々る炭化物を主体とする硬質相によってすぐれ
た而・j摩耗性を確保し、一方前記素地中に分散相とし
で存在するCuやSnの初晶、Cu −Sn合金やOu
−Sn −Fo金合金共晶によってすぐれた剛スカッ
フィング性と相手部材とのなじみ性を確保したものであ
る。しだがつて所望のすぐれた耐摩耗性を確保するには
、耐摩耗性に最も影響を及ぼす硬質相の割合を、面積率
で20係以」−とする必要があるが、面積率で6Q%を
越えた割合にすると相手攻撃性が急激に増大するように
なるので、硬質相の割合を面積率で20〜60係としな
けiLば々らない。B. Area ratio of hard phase The feed of the present invention consists of a matrix made entirely of mardensite, which has a relatively high Vickers hardness of 400 or more, which is a quenched or quenched/tempered structure, and a matrix containing fine grains in this matrix. , desirably has an average particle size of 10 to 50 μ7n, is uniformly dispersed, and ensures excellent abrasion properties due to the hard phase mainly consisting of carbides of the M2C type carbide and double carbide, while Primary crystals of Cu and Sn, Cu-Sn alloys and Ou exist as dispersed phases in
The -Sn-Fo gold alloy eutectic ensures excellent rigid scuffing properties and compatibility with the mating member. However, in order to ensure the desired excellent wear resistance, it is necessary to set the ratio of the hard phase that has the greatest effect on wear resistance to an area ratio of 20% or more. If the ratio exceeds , the aggressiveness of the opponent will increase rapidly, so unless the ratio of the hard phase is set to an area ratio of 20 to 60, iL will not be outstanding.
C理論密度比
制料の理論密度比が85tl)未満では、拐ネ:I中に
大きな空孔が存在するようになって、十分な強度を確保
することができないばか9でなく、この空孔のもつ切欠
効果によって素地が破壊され・やすくなり、ピソヂング
摩耗が発生しゃすくなることがら、その理論密度比を8
5飴以上と定めた。If the theoretical density ratio of the material C is less than 85 tl, large pores will exist in the hole, making it impossible to ensure sufficient strength. The notch effect of the material makes it easier to destroy the base material and cause pistoning wear, so the theoretical density ratio was set to 8.
It is set as 5 or more candies.
つぎに、この発明の制料金実施例により具体的に説明す
る。Next, the present invention will be specifically explained using a toll rate embodiment.
実施例
原料粉末として、いずれもM −t o Omeshノ
Mn : 0.6 % 、 MO: 0.3 q6含有
)粉末、アトマイズFe−Or −Mn −Mo合金(
C!r: 1%、Mn: Q6%、M。Examples of raw material powders include M-to-Omesh (Mn: 0.6%, MO: 0.3 q6-containing) powder, atomized Fe-Or-Mn-Mo alloy (
C! r: 1%, Mn: Q6%, M.
:0.3%含有)粉末、アトマイズFθ−Or −Mn
−M。:0.3%) powder, atomized Fθ-Or-Mn
-M.
合金(Cr:6%、 Mn : 0.6 % 、 Mo
: 0.3 %含イテ)粉末、さらに粒度−350m
esl〕のFe−P合金(p:17係含有)粉末、同一
250meGhのFo−P合金(P:27.5%含有)
粉末、同一35 (] meshのMo粉末、同一20
0meshのCu粉末、同一250meshのSn粉末
、同一200meshのFe −Mn合金(Mn゛78
係含有)粉含有以下いずれも粒度−100meshのF
e−V合金(V:6O%含有)粉末、ア1マイズIre
−Or−Mo−V合金(Cr : 3 %、 Mo :
0.3%、V:0.3%含有)粉末、 Fe−Or−
MoFe−0r−合金(Or: 4 %、 Mo: l
%、 Mn: 0.8%、 Zr :0.5%含有)
粉末、 Fe −Tj−合金(T:i、 : 40 %
含イj′)粉末、 Fe−Or−MoFe−0r−合金
(Or:4%、MOl %、 Mn: o、s %、
Hf: 1 %含有)粉末、Fe−NI)合金(Nb:
80%含有)粉末、および平均粒径:10μmの黒鉛粉
末を用意し、これら原料粉末をそれぞれ第1表に示され
る配合組成に配合し、潤2tJ剤としてステアリン酸亜
鉛:05%を加えてV型ミキサにて混合した後、3〜6
ton / alの範囲内の所定圧力にてプレス成形
して圧粉体とし、との圧粉体全真空中、寸たけ還元性雰
囲気中、1000〜1200℃の範囲内の所定温度に6
0分間保持の条件で焼結し、真空焼結の場合は、焼結後
、900〜1100℃の範囲内の所定温度から強制冷却
して焼入れし、寸だ還元性雰囲気焼結の場合d:、焼結
後、冷戻性雰囲気とし、800〜1000℃の範囲内の
所定温度から油冷して焼入れを行なうこと(/rCよっ
て、実質的に配合組成と同一の組成をもった本発明材料
1〜30および比較材料1〜15全それぞれ製造した。Alloy (Cr: 6%, Mn: 0.6%, Mo
: 0.3% powder), further particle size -350m
esl] Fe-P alloy (p: 17% content) powder, same 250meGh Fo-P alloy (P: 27.5% content)
Powder, same 35 (] Mesh Mo powder, same 20
0 mesh Cu powder, same 250 mesh Sn powder, same 200 mesh Fe-Mn alloy (Mn゛78
Contains powder) Particle size -100mesh F
e-V alloy (V: 60% content) powder, Amize Ire
-Or-Mo-V alloy (Cr: 3%, Mo:
0.3%, V: 0.3% content) powder, Fe-Or-
MoFe-0r-alloy (Or: 4%, Mo: l
%, Mn: 0.8%, Zr: 0.5%)
Powder, Fe-Tj-alloy (T:i, : 40%
Fe-Or-MoFe-0r-alloy (Or: 4%, MOL %, Mn: o, s %,
Hf: 1%) powder, Fe-NI) alloy (Nb:
80% containing) powder and graphite powder with an average particle size of 10 μm were prepared, and these raw material powders were blended into the composition shown in Table 1, and zinc stearate: 05% was added as a moisture 2tJ agent. After mixing in a mold mixer, 3 to 6
The green compact is press-formed at a predetermined pressure within the range of 1,000 to 1,200°C in a total vacuum, and at a predetermined temperature within the range of 1,000 to 1,200°C.
In the case of vacuum sintering, sintering is performed under the condition of holding for 0 minutes, and after sintering, forced cooling and quenching is performed from a predetermined temperature within the range of 900 to 1100 ° C. In the case of extremely reducing atmosphere sintering, d: After sintering, quenching is performed by oil cooling from a predetermined temperature in the range of 800 to 1000°C in a cooling atmosphere (/rC, therefore, the material of the present invention has substantially the same composition as the compounded composition). All of Comparative Materials 1 to 30 and Comparative Materials 1 to 15 were manufactured.
なお、比較材料1〜15ば、成分組成、硬質A目の面積
率、および理論密度比のうちの少なくともいずれかの条
件(第1表に※印を+1したもの)がこの発明の範囲か
ら外れた条件で製造されたものである。In addition, for Comparative Materials 1 to 15, at least one of the component composition, hard A-grain area ratio, and theoretical density ratio (+1 marked with * in Table 1) is out of the scope of the present invention. It was manufactured under the same conditions.
ついで、こ′の結果得られた本発明月別1〜30および
比較材料1〜15について、硬質相の面積率、理論密度
比、およびビッカース硬さを測定すると共に、と才I、
より自ポカ〕1;工/、、;ンのt−1ツカ−アノ・の
バット面に道1合した一プツシ(2を1月1iL、との
デツプ)1′、A金、「−1ノカーア−ノ・のジ5造1
1)に+C’J包み、この結果11tられたA−e合金
製ロソ′カー−j’ −ノ・を゛・l気fm OHCx
、 7ジyv′C絹込み、使fil オイy”、 L
’、P C+劣1’c M 、 liう1転数 850
r、 p、m、 、 運転11.1間 200時間の
条件て耐J¥7粍+4−試験を行ない、前記千ノフ(・
]の最大(Hy、粍深さと、相手部イ(たるチル処](
lIをMl」。Next, the area ratio of the hard phase, the theoretical density ratio, and the Vickers hardness were measured for the resulting invention materials 1 to 30 and comparative materials 1 to 15, and
1 push on the butt side of the t-1 of the t-1 (2 to 1 iL, depth) 1', A money, ``-1 Nokaa-no-no-ji 5-zo 1
1) wrapped in +C'J, resulting in 11 tons of A-e alloy Roso'car-j'-No.
, 7ji yv'C including silk, use fil oiy'', L
', P C + inferior 1'c M, li 1 rotation number 850
r, p, m, , 11.1 hours of operation, 200 hours J¥ 7mm + 4- test was conducted, and the above 1000mins (・
] maximum (Hy, depth and opponent part I (taru chill place) (
lI to Ml”.
(−た鋳ε失1(」カッ・(眉]♀′Jni且成は、0
33係、S]。(-ta caste loss 1 ('ka) (eyebrow) ♀' Jni and success is 0
Section 33, S].
2 %、Mn: 0.74. Cr: 0.5 %、白
r : (15%、F。2%, Mn: 0.74. Cr: 0.5%, white r: (15%, F.
]、・よぴ]不用避−1純物 残りからなり、かつfル
部の硬さは、ヒソカースr1更さて480)の晶Jえ乙
1・1、深さ全測定した。これらの」1]定結果4第2
ノ〈に示1−だ。], ・Yopi] Unnecessary Avoidance-1 Pure Matter The hardness of the part was measured at all depths of the crystals of Hysokase r1 and 480). These "1] definite results 4th 2nd
ノ〈shown in 1-.
第2表に示される結果か[:X)、本発明(”4月・l
[〜30ば、いずfi−も1ぐれ/こ耐摩柱性を41’
L、かつスカッフィングの発生もなく、しかも相手部
、(」とのなじみl’1.: 11ζすぐハ、ているの
て、相手攻撃性が−17しく低いものであるのに対して
、比較4″A別1〜15に魔らi17:、)ように、構
成成分の′)tシのいずノ圭かの成分含有量、硬Hpt
+11の曲伍率、および耶論密度比のつりのいずノ1
かの条件がこの発明の範I!tlから外J1゜ると、前
記のWfl″のうち少なくともいずJしかの!1711
′]が劣ったものになることが1す1らかである。な」
、・、−1記実施例では1.+:)J浦中のCUおよび
8↑)成分’5=、原]・−1粉末に配合し7てハイ」
さぜた場合に−)いで述−\たが、焼結後の(」イ・l
(−こi宣浸ン去(・でより含イ1させても」、いこと
(l;1、勿論である。The results shown in Table 2 [:
[~30%, Izufi-Mo1 Gravity/This wear resistance is 41'
L, there is no scuffing, and the opponent's familiarity with ('1.: 11ζ) is -17 and the opponent's aggressiveness is low at -17, whereas in comparison 4 ``A 1 to 15 to 17:,), the component content of the constituent components, hard Hpt
The curvature of +11 and the difference in the density ratio of 1
This condition is the scope of this invention! J1° outward from tl, at least one of the above Wfl''!1711
'] would be inferior. Na”
,.--In the first embodiment, 1. +:) J Uranaka's CU and 8 ↑) Ingredient '5=, Original]・-1 Mixed with powder and 7 is high.
When sintered, it is mentioned in -), but after sintering, it is
(-koi senin ni ni (・de yori ii 1 let me do it), igoto (l; 1, of course.
−1,、’vEのように、この発明t))Fe基焼結刊
11ハ、I゛ぐノしゾこ耐F%%玉・1〈1と面1スカ
ッフィングF1をイ]シフ、かて)相千丁父重1′1の
著[5,〈低いもの−Cあるので、眉に苛酷に:条千十
干でのf実用金子1義なくさ71つつあるター)J′f
【1内燃磯・閏や、・1然オ′・1として高鉛力ソリン
キ・1゜J’ Oガスをf小川する内燃機関なとの摺動
部]Aとし−Cmいた場合にもすぐれた111.能%、
’ J%期tic F−:、’、 −L) i a揮す
るのてパ・)る1、
1]i5願人 H菱金属株式会社-1,,'vE, this invention t)) Fe-based sintering publication 11 C, I゛gunoshiko resistance F%% ball 1〈1 and surface 1 scuffing F1〉 Schiff, or te) Authored by Aizencho Chiju 1'1 [5,〈Because there is a low-C, it is harsh on the eyebrows: f Practical Kaneko 1 Unreasonableness 71 is growing ter) J'f
[Sliding parts of internal combustion engines such as 1 internal combustion engine, leapfrog, 1 natural O', 1 high lead power solinki, 1° J' O gas] Excellent also when A is used - Cm 111. ability%,
' J% periodic F-:, ', -L) i a Exerting part 1, 1] i5 Applicant H Ryo Metal Co., Ltd.
Claims (2)
、 全含有し、残りがFeと不可避不純物からなる組成(以
上重量%)、並びに主としてマルテンーリーイトからな
る素地に、面積率で20〜60係の1三として炭化物か
らなる硬質相が微細均一に分11女した焼入れまたは焼
入れ・焼戻し組織を有し、75八つ理論密度比 8’5
%以上を有することを特徴と1−る内燃機関の摺動部材
用Fe基焼結材制。(1) Cr: Q, 5-s%, C: 2-5%, P: 0.02-5%, Mo: 0.05-3%, Mn: 0.05-3%, Cu and Sn One or two of the following: 5-20%
, the composition (wt%) consisting of all of the minerals and the remainder consisting of Fe and unavoidable impurities, and a fine and uniform hard phase consisting of carbide with an area ratio of 13 of 20 to 60 in the matrix mainly consisting of marten-leaite. It has a quenched or quenched/tempered structure with a theoretical density ratio of 75 to 8'5.
1. Fe-based sintered material system for sliding members of internal combustion engines, characterized in that it has a
0敷 を含イ1し、さらに、 V 、 Ti 、 Zr、 Hf、 およびNl−+の
う“らの1不f[/こ fL:l: 2 不重以 −l
: : 0.’0 2 〜5 裂 、を介イ1し、残り
がFeと不可避不純物からなる組成(以上重量%)、並
びに主としてマルテンサイトから々る素地に、面積率で
20〜60%の主として炭化物からなる硬質相が微細均
一に分散した焼入れまたは焼入れ・焼戻し組織を有し、
かつ理論密度比:85%以」二を有することを特徴とす
る内燃機関の摺動部利用Fe基焼結材料。(2) Or: 0.5-8%, 02-5 ratio, ],': 0.02-5 ratio, ↑10: 0.05-3 ratio, 1+4n: Q, 05-3%, Cu or 11 cities and 21 layers of Kobi Sn ゛5~2
Including 0 layers, and 1 of V, Ti, Zr, Hf, and Nl−+.
: : 0. '0 2 ~ 5 cracks, 1 through 1, with the remainder consisting of Fe and unavoidable impurities (wt%), and the base material is mainly martensite, and is mainly composed of carbides with an area ratio of 20 to 60%. It has a hardened or hardened/tempered structure in which the hard phase is finely and uniformly dispersed,
and a theoretical density ratio of 85% or more.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP15730983A JPS6050151A (en) | 1983-08-29 | 1983-08-29 | Fe-base sintered material for sliding member of internal-combustion engine |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP15730983A JPS6050151A (en) | 1983-08-29 | 1983-08-29 | Fe-base sintered material for sliding member of internal-combustion engine |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS6050151A true JPS6050151A (en) | 1985-03-19 |
JPH0215624B2 JPH0215624B2 (en) | 1990-04-12 |
Family
ID=15646851
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP15730983A Granted JPS6050151A (en) | 1983-08-29 | 1983-08-29 | Fe-base sintered material for sliding member of internal-combustion engine |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS6050151A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62271913A (en) * | 1986-04-11 | 1987-11-26 | Nippon Piston Ring Co Ltd | Builtup cam shaft |
JPH01160103U (en) * | 1988-04-27 | 1989-11-07 | ||
US7922836B2 (en) | 2004-04-22 | 2011-04-12 | Komatsu Ltd. | Ferrous abrasion resistant sliding material |
US7998238B2 (en) * | 2003-07-31 | 2011-08-16 | Komatsu Ltd. | Sintered sliding member and connecting device |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5729559A (en) * | 1980-07-29 | 1982-02-17 | Mitsubishi Metal Corp | Carbide dispersed type iron base sintered alloy having excellent antiwear property |
JPS5985847A (en) * | 1982-11-08 | 1984-05-17 | Mitsubishi Metal Corp | Fe-base sintered material for sliding member of internal-combustion engine |
-
1983
- 1983-08-29 JP JP15730983A patent/JPS6050151A/en active Granted
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5729559A (en) * | 1980-07-29 | 1982-02-17 | Mitsubishi Metal Corp | Carbide dispersed type iron base sintered alloy having excellent antiwear property |
JPS5985847A (en) * | 1982-11-08 | 1984-05-17 | Mitsubishi Metal Corp | Fe-base sintered material for sliding member of internal-combustion engine |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62271913A (en) * | 1986-04-11 | 1987-11-26 | Nippon Piston Ring Co Ltd | Builtup cam shaft |
JPH0542498B2 (en) * | 1986-04-11 | 1993-06-28 | Nippon Piston Ring Co Ltd | |
JPH01160103U (en) * | 1988-04-27 | 1989-11-07 | ||
US7998238B2 (en) * | 2003-07-31 | 2011-08-16 | Komatsu Ltd. | Sintered sliding member and connecting device |
US7922836B2 (en) | 2004-04-22 | 2011-04-12 | Komatsu Ltd. | Ferrous abrasion resistant sliding material |
US7967922B2 (en) | 2004-04-22 | 2011-06-28 | Komatsu Ltd. | Ferrous abrasion resistant sliding material |
Also Published As
Publication number | Publication date |
---|---|
JPH0215624B2 (en) | 1990-04-12 |
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