JPH05263200A - Sintered high speed steel excellent in seizing resistance and its manufacture - Google Patents
Sintered high speed steel excellent in seizing resistance and its manufactureInfo
- Publication number
- JPH05263200A JPH05263200A JP4091719A JP9171992A JPH05263200A JP H05263200 A JPH05263200 A JP H05263200A JP 4091719 A JP4091719 A JP 4091719A JP 9171992 A JP9171992 A JP 9171992A JP H05263200 A JPH05263200 A JP H05263200A
- Authority
- JP
- Japan
- Prior art keywords
- speed steel
- sintered
- high speed
- powder
- sintering
- 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.)
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Links
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は焼結高速度鋼に関するも
のであり、さらに詳しく述べるならば耐焼付性に優れた
焼結高速度鋼及びその製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a sintered high speed steel, and more particularly to a sintered high speed steel excellent in seizure resistance and a method for producing the same.
【０００２】[0002]
【従来の技術】溶製高速度鋼のすぐれた高温強度や耐摩
耗性を焼結材にもたせた焼結高速度鋼の用途開発が期待
されている。一方ＨＩＰ処理を行った切削用焼結高速度
鋼は、ＨＲＣ７０クラスの硬度を有するものが工具とし
て市販されている。2. Description of the Related Art Application of sintered high-speed steel, which has excellent high-temperature strength and wear resistance of molten high-speed steel, has been expected. On the other hand, the HIP-treated sintered high-speed steel for cutting has a hardness of HRC70 class and is commercially available as a tool.
【０００３】[0003]
【発明が解決しようとする課題】鉄系材料は強度がある
ために強度面では優れた摺動材料であり、したがって上
記の焼結高速度鋼は硬度が非常に高く、潤滑下では摺動
特性が良好であると考えられる。しかしながら、摺動部
材の相手材が鉄系材料であると面圧が高い摺動条件では
油膜切れにより鉄同士の摺動を起こし焼付が発生しやす
いので、上記焼結高速度鋼は焼付の面で問題がある。The iron-based material is a sliding material excellent in strength because of its strength. Therefore, the above-mentioned sintered high-speed steel has a very high hardness and the sliding characteristics under lubrication. Is considered to be good. However, when the mating material of the sliding member is an iron-based material, under a sliding condition where the surface pressure is high, sliding of the irons easily occurs due to oil film breakage, and seizure easily occurs. I have a problem with.
【０００４】一方、鉄同士が摺動する場合、摺動部材の
鉄系材料に銅を介在させると焼付を防止できることは良
く知られている。したがって焼結高速度鋼に銅を溶浸す
ることが耐焼付性向上に有効であると考えられる。しか
し焼結高速度鋼に本来の材料特性をもたせるには焼結を
１１００〜１３００℃で行わなければならず、すると空
孔が相互につながらい孤立した閉空孔（クローズドポ
ア）になってしまうために銅の溶浸ができない。よっ
て、焼結温度を低くして網状の連続空孔に銅を溶浸した
焼結高速度鋼が発表されているが、耐摩耗性、強度、高
温強度などが圧延・鍛造材に比べて著しく劣っていた。On the other hand, when irons slide on each other, it is well known that seizure can be prevented by interposing copper in the iron-based material of the sliding member. Therefore, it is considered that infiltration of copper into sintered high-speed steel is effective in improving seizure resistance. However, in order to give the sintered high-speed steel the original material properties, it is necessary to perform sintering at 1100 to 1300 ° C, and then the pores will connect to each other and become isolated closed pores (closed pores). Infiltration of copper is not possible. Therefore, sintered high-speed steel in which copper is infiltrated into mesh-like continuous pores at a low sintering temperature has been announced, but its wear resistance, strength, high temperature strength, etc. are significantly higher than those of rolled and forged materials. It was inferior.
【０００５】よって本発明は、摺動特性が優れたＣｕ介
在型焼結高速度鋼ならびにその製造方法を提供すること
を目的とする。Therefore, it is an object of the present invention to provide a Cu-intercalated sintered high-speed steel having excellent sliding properties and a method for producing the same.
【０００６】[0006]
【課題を解決するための手段】本発明は、第一に、重量
％で、Ｃ：０．８０〜１．６％，Ｃｒ：３〜６％、Ｗ＋
２Ｍｏ：１０〜２０％、Ｖ：１〜５％を必須成分として
含み、残部が実質的にＦｅからなる高速度鋼焼結合金基
地に微細なＣｕ相が均一に分散され、焼結気孔がクロー
ズドポアの状態でありかつＣｕの含有量が１〜８％であ
ることを特徴とする焼結高速度鋼に関し、また 第二
に、重量％で、Ｃ：０．８０〜１．６％，Ｃｒ：３〜６
％、Ｗ＋２Ｍｏ：１０〜２０％、Ｖ：１〜５％を必須成
分として含み、残部が実質的にＦｅからなる高速度鋼粉
末とＣｕ粉末を、Ｃｕの含有量が１〜８％となるように
混合し、混合物を圧粉しそしてＣｕの液相発生温度以上
で焼結し、Ｃｕを基地に完全に固溶させると共に少なく
ともＣｕの析出温度をガス冷却以上の速度で冷却し、得
られた焼結材にＣｕ析出熱処理を施すことを特徴とする
焼結高速度鋼の製造方法に関する。According to the present invention, firstly, by weight, C: 0.80 to 1.6%, Cr: 3 to 6%, W +.
2Mo: 10 to 20%, V: 1 to 5% as essential components, the balance is a high-speed steel sintered alloy matrix consisting essentially of Fe, fine Cu phase is uniformly dispersed, and the sintered pores are closed. A sintered high-speed steel characterized by being in a pore state and having a Cu content of 1 to 8%, and secondly, in% by weight, C: 0.80 to 1.6%, Cr : 3 to 6
%, W + 2Mo: 10 to 20%, V: 1 to 5% as essential components, and the balance is high-speed steel powder and Cu powder consisting essentially of Fe, so that the Cu content is 1 to 8%. The resulting mixture was mixed with, powdered and sintered at a temperature above the liquid phase generation temperature of Cu to completely dissolve Cu in the matrix and to cool at least the precipitation temperature of Cu at a rate of gas cooling or higher. The present invention relates to a method for producing a sintered high speed steel, which comprises subjecting a sintered material to a Cu precipitation heat treatment.
【０００７】以下、本発明の構成を説明する。高速度鋼
は、公知のものあるいはＪＩＳなどの工業規格で規定さ
れているものであればよいが、摺動特性の面から以下の
ように組成を限定した。Ｃ（炭素）が０．８０％未満で
あると、焼入時にフエライトが生成することがありまた
炭化物の量が少なくなり、一方１．６％を越えると焼結
時に液相が多く発生するなどの欠点が現れるので、０．
８〜１．６％の範囲に限定した。The structure of the present invention will be described below. The high-speed steel may be any known steel or one defined by industrial standards such as JIS, but the composition is limited as follows in terms of sliding characteristics. If C (carbon) is less than 0.80%, ferrite may be generated during quenching and the amount of carbides may be reduced, while if it exceeds 1.6%, a large amount of liquid phase may be generated during sintering. Since the drawback of 0 appears.
It was limited to the range of 8 to 1.6%.
【０００８】ＣｒはＦｅ基地を強化するとともに熱処理
性がある炭化物を適量生成するために３％以上が必要で
あり、一方６％を越えると、Ｗ，Ｍｏなどの特殊炭化物
の量が少なくなりまたフェライトが生成することがある
ので、３〜６％の範囲に限定した。[0008] Cr needs to be 3% or more in order to strengthen the Fe base and to generate an appropriate amount of carbide having heat-treatability. On the other hand, if it exceeds 6%, the amount of special carbides such as W and Mo decreases, and Since ferrite may be formed, it is limited to the range of 3 to 6%.
【０００９】Ｖは硬度が高くかつ熱的に安定な特殊炭化
物を適量生成するために１％以上必要であり、一方６％
を越えると炭化物が粗大化し、かつフェライトを生成す
ることがあるので１〜６％の範囲に限定した。V is required to be 1% or more in order to form a proper amount of special carbide having high hardness and thermal stability, while 6% is required.
If it exceeds 0.1%, the carbides may be coarsened and ferrite may be formed, so the content is limited to 1 to 6%.
【００１０】ＭｏとＷはＦｅ基地を強化するとともに二
次硬化をもたらす特殊炭化物を形成するために、Ｗおよ
び／またはＭｏがＷ＋２Ｍｏの等量で１０％以上が必要
であり、一方２０％を越えると炭化物が粗大化し、かつ
フェライトが生成することがあるので、１０〜２０％の
範囲に限定した。In order to strengthen the Fe base and form a special carbide which causes secondary hardening, Mo and W must have an amount of W and / or Mo in the same amount as W + 2Mo in an amount of 10% or more, while exceeding 20%. Since carbides may coarsen and ferrite may be generated, the content is limited to 10 to 20%.
【００１１】また、本発明の必須添加元素としてのＣｕ
は１〜８％の範囲に限定される。Ｃｕの含有量が１％未
満であると後述の効果がなく、一方８％を越えると添加
されたＣｕが焼結温度におけるＣｕの固溶限を越えるた
めに過剰な液相が網目状に分布し、高速度鋼自身の焼結
を妨げさらにＣｕ相が粗大化する。好ましくは３〜８％
のＣｕ範囲である。Cu as an essential additive element of the present invention
Is limited to the range of 1 to 8%. If the content of Cu is less than 1%, there is no effect described later, while if it exceeds 8%, the added Cu exceeds the solid solubility limit of Cu at the sintering temperature, and an excessive liquid phase is distributed in a network. However, the sintering of the high speed steel itself is hindered and the Cu phase becomes coarser. Preferably 3-8%
Is the Cu range.
【００１２】上記組成の他に、オーステナイトにおける
Ｗ，Ｍｏの溶解度を高めるＣｏを３０％以下含有させる
ことができる。さらに、Ｔｉ，Ｚｒ，Ｎｉ，Ｍｎ，Ｓｉ
などを少量添加しても上述の各元素の作用を妨げないの
で、これらの元素も添加してもよい。ただし、ＮｉはＣ
ｕの析出を妨げるの１％以下にする必要がある。In addition to the above composition, Co which enhances the solubility of W and Mo in austenite can be contained in an amount of 30% or less. In addition, Ti, Zr, Ni, Mn, Si
These elements may also be added because addition of a small amount does not interfere with the action of each element described above. However, Ni is C
It must be 1% or less to prevent the precipitation of u.
【００１３】本発明の焼結高速度鋼の組織が特徴とする
ところは微細なＣｕ相が均一に分散しているところにあ
る。すなわち、Ｃｕは焼結温度において析出しないよう
にし、一旦基地に固溶したＣｕを室温まで過飽和の状態
で維持し、その後の熱処理により析出させることによ
り、微細かつ均一なＣｕ析出相を得る。したがって、Ｃ
ｕ相は高温で形成された一次炭化物及び高温からの冷却
中に形成された一次炭化物もしくは二次炭化物より平均
寸法が微細であり、高速度鋼の焼戻し炭化物と同等もし
くはそれ以下の平均寸法を有する。The structure of the sintered high speed steel of the present invention is characterized in that fine Cu phase is uniformly dispersed. That is, Cu is prevented from precipitating at the sintering temperature, Cu once solid-dissolved in the matrix is maintained in a supersaturated state up to room temperature, and then it is precipitated by heat treatment to obtain a fine and uniform Cu precipitation phase. Therefore, C
The u phase has a smaller average size than primary carbides formed at high temperatures and primary or secondary carbides formed during cooling from high temperatures, and has an average size equal to or less than the tempered carbides of high speed steels. ..
【００１４】本発明の製造方法は、上記組成を有する高
速度鋼粉末と銅粉末を通常の粉末冶金法で混合し圧粉し
た後、銅の液相発生温度（１０８３℃）以上で焼結しか
つＣｕを基地に完全に固溶させ、その後少なくともＣｕ
の析出温度域を焼結材料をガス冷却以上の冷却速度で冷
却し、続いて銅の析出処理を行うことを特徴とする。高
速度鋼粉末は表面のコンタミネーションにより、比較的
低い温度で粉末表面に液相を発生するので、経済性を考
えて１２００℃以下の温度で焼結するのが好ましい。焼
結温度において溶解した銅は高速度鋼粉末粒子の周囲か
らその中に固溶し、拡散する。そのために必要な焼結時
間は銅の量にもよるが一般に３０分以上である。In the production method of the present invention, the high-speed steel powder having the above composition and the copper powder are mixed and pressed by an ordinary powder metallurgy method, and then sintered at a liquidus generation temperature of copper (1083 ° C.) or higher. Moreover, Cu is completely dissolved in the base material, and then at least Cu
Is characterized in that the sintering material is cooled at a cooling rate higher than that of the gas cooling in the precipitation temperature range of 1, and then the copper precipitation treatment is performed. Since high-speed steel powder generates a liquid phase on the surface of the powder at a relatively low temperature due to surface contamination, it is preferable to sinter at a temperature of 1200 ° C. or less in consideration of economy. The molten copper at the sintering temperature forms a solid solution and diffuses into the high speed steel powder particles from the surroundings. The sintering time required for this is generally 30 minutes or more, although it depends on the amount of copper.
【００１５】焼結に続いて冷却を行うが、この際少なく
とも銅の析出温度域をガス冷却以上の冷却速度で冷却を
行う。銅はＦｅ基地が一部フェライト化すると固溶度が
急激に低下するので、平衡状態図よりＦｅ基地の変態が
起こる温度（主としてＣ量により大きく変化する）を基
準として急冷開始温度を定める。続いて高速度鋼の標準
的熱処理である焼入を行ってもよいが、焼結とその後の
急冷により焼入を兼ねさせることもできる。続いて銅の
析出処理を４００〜７００℃で行う。なお高速度鋼の標
準的な熱処理である焼き戻しは一般に５００〜６００℃
の温度で行われ、この温度は銅の析出熱処理温度に含ま
れるので、焼戻しと析出処理を同時に行うことができ
る。Cooling is performed after the sintering. At this time, at least the copper precipitation temperature range is cooled at a cooling rate higher than that of gas cooling. Since the solid solubility of copper sharply decreases when the Fe base partly becomes ferritic, the quenching start temperature is determined from the equilibrium diagram based on the temperature at which the transformation of the Fe base occurs (mainly largely changes depending on the amount of C). Subsequently, quenching, which is a standard heat treatment of high-speed steel, may be performed, but it is also possible to perform both quenching by sintering and subsequent quenching. Subsequently, a copper precipitation treatment is performed at 400 to 700 ° C. Note that tempering, which is a standard heat treatment for high-speed steel, is generally 500 to 600 ° C.
Since this temperature is included in the copper precipitation heat treatment temperature, tempering and precipitation treatment can be performed simultaneously.
【００１６】焼結高速度鋼と相手材の摺動面にＣｕを介
在させる方法として、微細かつ均一に高速度鋼基地に析
出したＣｕ相を使用することにより、高速度鋼の特性を
十分に活用することができる。すなわち、一次、二次、
焼き戻し炭化物を十分に生成させ、焼入れ及び焼戻しに
より焼入れ及び焼戻しマルテンサイトを十分に形成さ
せ、さらに高温焼結を行うことにより焼結を促進し焼結
材の強度を高めることができる。本発明が特徴とするＣ
ｕの析出は上記いずれの作用も妨げるものではなく、逆
にこれらにより妨げられない。以下実施例により本発明
をより具体的に説明する。As a method of interposing Cu on the sliding surface between the sintered high speed steel and the mating material, the Cu phase precipitated finely and uniformly in the high speed steel matrix is used to obtain sufficient characteristics of the high speed steel. Can be utilized. That is, primary, secondary,
It is possible to sufficiently generate tempered carbides, sufficiently form quenching and tempering martensite by quenching and tempering, and further perform high-temperature sintering to promote sintering and increase strength of the sintered material. C characterized by the present invention
The precipitation of u does not hinder any of the above actions, and conversely is not hindered by them. Hereinafter, the present invention will be described more specifically with reference to Examples.
【００１７】[0017]
【実施例】粒度が１５０〜２００メッシュにピークをも
つＳＫＨ９相当の高速度鋼粉末（組成を表１に示す）に
２００メッシュアンダ−の銅粉を５％加え、さらに金型
成型の際の抜けを良くするために潤滑剤としてステアリ
ン酸亜鉛を０．６％加えた混合粉をプレスにて７ｔ／ｃ
ｍ2 の成形圧力で成形し、成形体を作成した。Example: 5% of 200 mesh under copper powder was added to SKH9 high speed steel powder (composition shown in Table 1) corresponding to SKH9 having a particle size peak at 150 to 200 mesh, and the powder was removed during molding. In order to improve the temperature, the mixed powder containing 0.6% zinc stearate as a lubricant was pressed at 7t / c.
Molding was performed at a molding pressure of m 2 to prepare a molded body.
【００１８】この成形体を真空雰囲気下で６５０℃で１
時間脱蝋した後、１２５０℃で６０分間保持し、焼結を
行った。焼結後９００℃まで炉冷し、９００℃より窒素
ガス冷却した。続いて５５０℃で１時間焼き戻し（Ｃｕ
の析出熱処理）を行った。This molded body was subjected to 1 at 650 ° C. in a vacuum atmosphere.
After dewaxing for an hour, it was held at 1250 ° C. for 60 minutes for sintering. After sintering, the furnace was cooled to 900 ° C., and nitrogen gas was cooled from 900 ° C. Then, temper at 550 ° C for 1 hour (Cu
Precipitation heat treatment).
【００１９】こうして作成した素材を所定寸法に加工
後、超高圧摩擦試験機により以下に示す試験条件で焼付
荷重を測定した。結果を表２に示す。 摺動速度：１０ｍ／ｓｅｃ 潤滑油：パラフィン系冷凍機油 潤滑油量：２５０ｃｃ／ｍｉｎ 潤滑油温：５０℃ 摺動面粗さ：１〜２ｓ 初期荷重：２０ｋｇ／ｃｍ2 荷重速度：１０ｋｇ／ｃｍ2 ／３ｍｉｎ 相手材 ：ＳＵＪ２ 焼付の判定：摩擦力が５ｋｇになった時点で焼付と判定After the material thus prepared was processed into a predetermined size, the seizure load was measured by an ultrahigh pressure friction tester under the following test conditions. The results are shown in Table 2. Sliding speed: 10 m / sec Lubricating oil: Paraffinic refrigerating machine oil Lubricant oil amount: 250 cc / min Lubricating oil temperature: 50 ° C. Sliding surface roughness: 1-2 s Initial load: 20 kg / cm 2 Load speed: 10 kg / cm 2 / 3min Counterpart material: SUJ2 Seizure judgment: Judged as seizure when the friction force reached 5 kg
【００２０】 表１ 化学成分（％） 物 性 Ｃ Ｃｒ Ｍｏ Ｖ Ｗ Ｃｕ 密度 硬さ 引張強さ 空孔 比較材 0.85 4.0 5.0 2.0 6.0 − 7.24 27.3 1230 本発明材 0.81 3.8 4.75 1.9 5.7 5.0 7.41 28.8 1440 備考：密度の単位はｇ／ｃｍ3 ，硬さの単位はＨＲＣ、
引張強さの単位はＭＰａ、空孔は体積％である。 Table 1 Chemical composition (%) Physical properties C Cr Mo V W Cu Density Hardness Tensile strength Porosity comparison material 0.85 4.0 5.0 2.0 6.0 − 7.24 27.3 1230 Invention material 0.81 3.8 4.75 1.9 5.7 5.0 7.41 28.8 1440 Remarks : The unit of density is g / cm 3 , the unit of hardness is HRC,
The unit of tensile strength is MPa, and voids are volume%.
【００２１】 表２ 焼付荷重（ｋｇｆ／ｃｍ2 ） 比較材 ８０、１００、１２５：平均１０１．７ 本発明材 １４５、１８０、２３０：平均１８５．０ 本発明材はＣｕを添加しない焼結高速度鋼に比べて焼付
荷重が高く摺動特性に優れていることが明らかである。 Table 2 Baking load (kgf / cm 2 ) Comparative material 80, 100, 125: Average 101.7 Inventive material 145, 180, 230: Average 185.0 Inventive material : High sintering rate without addition of Cu It is clear that the seizure load is higher and the sliding characteristics are superior to steel.
【００２２】[0022]
【発明の効果】以上説明した本発明の焼結高速度鋼は接
触面圧が高い条件下での摺動特性が優れているので、コ
ンプレッサ部品、軸受などの用途に適している。また本
発明の方法は、ＨＩＰなどの方法によらない通常の粉末
冶金法であるので、工業的に実施が容易である。The sintered high-speed steel of the present invention described above has excellent sliding characteristics under conditions of high contact surface pressure, and is suitable for applications such as compressor parts and bearings. Further, since the method of the present invention is a usual powder metallurgy method that does not depend on a method such as HIP, it is industrially easy to carry out.
Claims (2)
ｒ：３〜６％、Ｗ＋２Ｍｏ：１０〜２０％、Ｖ：１〜５
％を必須成分として含み、残部が実質的にＦｅからなる
高速度鋼焼結合金からなる基地に微細なＣｕ相が均一に
分散され、焼結気孔がクローズドポア状でありかつＣｕ
の含有量が１〜８％であることを特徴とする耐焼付性が
すぐれた焼結高速度鋼。1. By weight%, C: 0.80 to 1.6%, C
r: 3 to 6%, W + 2Mo: 10 to 20%, V: 1 to 5
% As an essential component, the fine Cu phase is uniformly dispersed in a matrix made of a high speed steel sintered alloy, the balance of which is substantially Fe, and the sintered pores are closed pores and Cu.
The high-speed sintered steel with excellent seizure resistance, characterized in that the content of 1 to 8%.
ｒ：３〜６％、Ｗ＋２Ｍｏ：１０〜２０％、Ｖ：１〜５
％を必須成分として含み、残部が実質的にＦｅからなる
高速度鋼粉末とＣｕ粉末を、Ｃｕの含有量が１〜８％と
なるように混合し、混合粉を圧粉しそしてＣｕの液相発
生温度以上で焼結し、Ｃｕを基地に完全に固溶させると
共に少なくともＣｕの析出温度域をガス冷却以上の速度
で冷却し、得られた焼結材にＣｕ析出熱処理を施すこと
を特徴とする耐焼付性にすぐれた焼結高速度鋼の製造方
法。2. C: 0.80 to 1.6%, C by weight%
r: 3 to 6%, W + 2Mo: 10 to 20%, V: 1 to 5
% As an essential component, and a high-speed steel powder, the balance of which is substantially Fe, and Cu powder are mixed so that the Cu content is 1 to 8%, the mixed powder is compacted, and the liquid of Cu is mixed. Characterized by sintering above the phase generation temperature, completely dissolving Cu in the matrix, cooling at least the Cu precipitation temperature range at a rate of gas cooling or higher, and subjecting the resulting sintered material to Cu precipitation heat treatment. And a method for producing a sintered high-speed steel having excellent seizure resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP09171992A JP3399972B2 (en) | 1992-03-17 | 1992-03-17 | Sintered high-speed steel with excellent seizure resistance and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP09171992A JP3399972B2 (en) | 1992-03-17 | 1992-03-17 | Sintered high-speed steel with excellent seizure resistance and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05263200A true JPH05263200A (en) | 1993-10-12 |
| JP3399972B2 JP3399972B2 (en) | 2003-04-28 |
Family
ID=14034320
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP09171992A Expired - Fee Related JP3399972B2 (en) | 1992-03-17 | 1992-03-17 | Sintered high-speed steel with excellent seizure resistance and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3399972B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08109450A (en) * | 1994-10-12 | 1996-04-30 | Hitachi Powdered Metals Co Ltd | Wear resistant sintered alloy for oilless bearing |
| JP2000017369A (en) * | 1998-07-06 | 2000-01-18 | Riken Corp | Wear resistant sintered alloy and its production |
| JP2005264325A (en) * | 2004-02-18 | 2005-09-29 | Sumitomo Denko Shoketsu Gokin Kk | Sintered high speed steel and method for manufacturing the same, and sliding components made of the sintered high speed steel |
| JP2018145462A (en) * | 2017-03-02 | 2018-09-20 | 株式会社デンソー | Iron-based sintered alloy and manufacturing method therefor |
-
1992
- 1992-03-17 JP JP09171992A patent/JP3399972B2/en not_active Expired - Fee Related
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08109450A (en) * | 1994-10-12 | 1996-04-30 | Hitachi Powdered Metals Co Ltd | Wear resistant sintered alloy for oilless bearing |
| JP2000017369A (en) * | 1998-07-06 | 2000-01-18 | Riken Corp | Wear resistant sintered alloy and its production |
| JP2005264325A (en) * | 2004-02-18 | 2005-09-29 | Sumitomo Denko Shoketsu Gokin Kk | Sintered high speed steel and method for manufacturing the same, and sliding components made of the sintered high speed steel |
| JP2018145462A (en) * | 2017-03-02 | 2018-09-20 | 株式会社デンソー | Iron-based sintered alloy and manufacturing method therefor |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3399972B2 (en) | 2003-04-28 |
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