JPH09157805A - High strength iron base sintered alloy - Google Patents
High strength iron base sintered alloyInfo
- Publication number
- JPH09157805A JPH09157805A JP31537495A JP31537495A JPH09157805A JP H09157805 A JPH09157805 A JP H09157805A JP 31537495 A JP31537495 A JP 31537495A JP 31537495 A JP31537495 A JP 31537495A JP H09157805 A JPH09157805 A JP H09157805A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- powder
- sintered alloy
- iron
- based sintered
- 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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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、ギヤ、ロータ
ー、プーリー、スプロケット、バルブシートなどの機械
部品の材料として用いられる高強度鉄基焼結合金に関す
るものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength iron-based sintered alloy used as a material for mechanical parts such as gears, rotors, pulleys, sprockets and valve seats.
【０００２】[0002]
【従来の技術】従来、ギヤ、ローター、プーリー、スプ
ロケット、バルブシートなどの機械部品の部材として、
ＮｉおよびＣｕのうち少なくとも１種：１〜４重量％、
Ｍｏ：０．５〜４重量％、Ｃ：０．５〜０．９重量％を
含有し、残りがＦｅおよび不可避不純物からなる組成を
有する鉄基焼結合金が知られており、この鉄基焼結合金
は、Ｃ：０．０５％以下、Ｍｏ：０．２〜２重量％、Ｏ
2 ：０．２重量％以下、残部：Ｆｅと２重量％以下の不
可避不純物からなる低合金鉄粉末に、０．２〜１．０重
量％の黒鉛粉末と、Ｎｉ粉末およびＣｕ粉末のうち少な
くとも１種：０．５〜４．０重量％を添加混合し、つい
でこの混合粉末を所定形状に圧粉成形した後、非酸化雰
囲気中で焼結することにより焼結体を作製し、この焼結
体を完全にオーステナイトになる温度領域（この温度
は、通常、オーステナイト変態温度＋５０℃よりも高い
温度であり、以下、完全オーステナイト化温度という）
に加熱保持した後、油焼き入れし、ついで低温焼戻し処
理することにより製造されることも知られている。かか
る熱処理して得られた焼結合金はマルテンサイト組織を
有している（例えば、特公平５−６１３３９号公報参
照）。2. Description of the Related Art Conventionally, as members of mechanical parts such as gears, rotors, pulleys, sprockets and valve seats,
At least one of Ni and Cu: 1 to 4% by weight,
An iron-based sintered alloy containing Mo: 0.5 to 4% by weight, C: 0.5 to 0.9% by weight, and the balance of Fe and inevitable impurities is known. The sintered alloy is C: 0.05% or less, Mo: 0.2 to 2% by weight, O
2 : 0.2% by weight or less, the balance: Fe and 2% by weight or less of a low alloy iron powder consisting of inevitable impurities, 0.2 to 1.0% by weight of graphite powder, and at least Ni powder and Cu powder. 1 type: 0.5 to 4.0% by weight is added and mixed, and then the mixed powder is compacted into a predetermined shape, and then sintered in a non-oxidizing atmosphere to prepare a sintered body, and this sintered body is baked. Temperature range where the aggregate becomes completely austenite (this temperature is usually higher than the austenite transformation temperature + 50 ° C., hereinafter referred to as complete austenitization temperature)
It is also known that it is produced by heating and holding at 0 ° C., oil quenching, and then low temperature tempering treatment. The sintered alloy obtained by such heat treatment has a martensitic structure (see, for example, Japanese Patent Publication No. 5-61339).
【０００３】[0003]
【発明が解決しようとする課題】しかし、近年、作業の
高性能化、高出力化および高速化にともない、機械装置
に組み込まれている機械部品は従来よりも一段と苛酷な
条件での繰り返し負荷が加えられ、このため、高強度の
鉄基焼結合金からなる機械部品が求められている。However, in recent years, as the performance, output and speed of work have become higher, the mechanical parts incorporated in the machine are subject to repeated load under more severe conditions than before. In addition, therefore, there is a demand for machine parts made of high-strength iron-based sintered alloys.
【０００４】[0004]
【課題を解決するための手段】そこで、本発明者らは、
上述のような観点から、機械部品の材料として、従来よ
りも高強度の鉄基焼結合金を得るべく研究を行った結
果、焼結して得られたＮｉ：１〜４重量％および／また
はＣｕ：１〜４重量％、Ｍｏ：０．５〜４重量％、Ｃ：
０．５〜０．９重量％を含有し、残りがＦｅおよび不可
避不純物からなる組成の鉄基焼結体を室温まで炉冷した
後、再び、オーステナイト変態温度〜オーステナイト変
態温度＋５０℃の温度領域（以下、オーステナイト直上
温度という）に加熱保持したのち、さらに油焼き入れし
た後焼戻し処理すると、マルテンサイト素地中に平均粒
径：０．１〜５μｍの微細な粒状炭化物が分散した組織
が生成され、この粒状炭化物が分散した組織を有する鉄
基焼結合金は、従来よりも強度が一層向上するという知
見を得たのである。Means for Solving the Problems Accordingly, the present inventors have:
From the above viewpoints, as a result of conducting research to obtain an iron-based sintered alloy having higher strength than conventional materials as a material for machine parts, Ni obtained by sintering: 1 to 4% by weight and / or Cu: 1 to 4% by weight, Mo: 0.5 to 4% by weight, C:
After the iron-based sintered body containing 0.5 to 0.9% by weight and the balance consisting of Fe and unavoidable impurities is furnace-cooled to room temperature, the temperature range is again from austenite transformation temperature to austenite transformation temperature + 50 ° C. After heating and holding (hereinafter referred to as a temperature just above austenite), further oil quenching and then tempering treatment, a structure in which fine granular carbides with an average particle size of 0.1 to 5 μm are dispersed in the martensite matrix is generated. It has been found that the iron-based sintered alloy having a structure in which the granular carbides are dispersed has further improved strength as compared with the conventional one.
【０００５】この発明は、かかる知見にもとづいて成さ
れたものであって、（１） Ｎｉ：１〜４重量％、Ｍ
ｏ：０．５〜４重量％、Ｃ：０．５〜０．９重量％を含
有し、残りがＦｅおよび不可避不純物からなる組成、並
びにマルテンサイト素地中に平均粒径：０．１〜５μｍ
の粒状炭化物が分散した組織を有する高強度鉄基焼結合
金、（２） Ｃｕ：１〜４重量％、Ｍｏ：０．５〜４重
量％、Ｃ：０．５〜０．９重量％を含有し、残りがＦｅ
および不可避不純物からなる組成、並びにマルテンサイ
ト素地中に平均粒径：０．１〜５μｍの粒状炭化物が分
散した組織を有する高強度鉄基焼結合金、（３） Ｎ
ｉ：１〜４重量％、Ｃｕ：１〜４重量％、Ｍｏ：０．５
〜４重量％、Ｃ：０．５〜０．９重量％を含有し、残り
がＦｅおよび不可避不純物からなる組成、並びにマルテ
ンサイト素地中に平均粒径：０．１〜５μｍの粒状炭化
物が分散した組織を有する高強度鉄基焼結合金、に特徴
を有するものである。The present invention was made on the basis of such findings, and (1) Ni: 1 to 4% by weight, M
O: 0.5 to 4% by weight, C: 0.5 to 0.9% by weight, the balance consisting of Fe and unavoidable impurities, and average particle size in the martensite matrix: 0.1 to 5 μm
A high-strength iron-based sintered alloy having a structure in which the granular carbide of (2) Cu: 1-4 wt%, Mo: 0.5-4 wt%, C: 0.5-0.9 wt% Contains, balance Fe
And a composition consisting of inevitable impurities, and a high-strength iron-based sintered alloy having a structure in which granular carbide having an average particle size of 0.1 to 5 μm is dispersed in a martensite matrix, (3) N
i: 1 to 4% by weight, Cu: 1 to 4% by weight, Mo: 0.5
˜4% by weight, C: 0.5 to 0.9% by weight, the rest consisting of Fe and inevitable impurities, and granular carbide with an average particle size of 0.1 to 5 μm dispersed in the martensite matrix. It is characterized by a high-strength iron-based sintered alloy having the above structure.
【０００６】この発明のマルテンサイト素地中に粒状炭
化物が分散した組織を有する高強度鉄基焼結合金は、原
料粉末として、Ｆｅ−Ｍｏ粉末、Ｎｉ粉末、Ｃｕ粉末お
よび黒鉛粉末を用意し、これら原料粉末を金型成形時の
潤滑剤であるステアリン酸亜鉛粉末とともに混合しプレ
ス成形して圧粉体を作製し、得られた圧粉体を窒素雰囲
気中で焼結して焼結体を作製し、この焼結体を室温まで
空冷する。このようにして得られた焼結体を、その後、
窒素雰囲気中、オーステナイト直上温度に加熱保持した
のち、さらに焼入れおよび焼戻し処理することにより製
造される。The high-strength iron-based sintered alloy of the present invention having a structure in which granular carbides are dispersed in the martensite matrix is prepared by using Fe-Mo powder, Ni powder, Cu powder and graphite powder as raw material powders. Raw material powder is mixed with zinc stearate powder, which is a lubricant at the time of die molding, and press-molded to produce a green compact, and the obtained green compact is sintered in a nitrogen atmosphere to produce a sintered body. Then, this sintered body is air-cooled to room temperature. The sintered body thus obtained is then
It is manufactured by heating and holding at a temperature just above austenite in a nitrogen atmosphere, and then further quenching and tempering.
【０００７】つぎに、この発明の鉄基焼結合金の成分組
成および組織を上記のごとく限定した理由について説明
する。Next, the reasons for limiting the component composition and structure of the iron-based sintered alloy of the present invention as described above will be explained.
【０００８】Ａ：成分組成 （ａ）Ｎｉ Ｎｉは、若干量のオーステナイト残留させ、疲労強度お
よび靭性を向上させる作用があるが、その含有量が１重
量％未満ではその効果が十分でなく、一方、４重量％を
越えて含有してもその効果が少ないところから、Ｎｉの
含有量は、１〜４重量％に定めた。Ｎｉの含有量の一層
好ましい範囲は２〜３重量％である。A: Component composition (a) Ni Ni Ni has the effect of allowing a small amount of austenite to remain and improving fatigue strength and toughness, but if its content is less than 1% by weight, its effect is insufficient. Since the effect is small even if the content exceeds 4% by weight, the content of Ni is set to 1 to 4% by weight. A more preferable range of the Ni content is 2-3% by weight.
【０００９】（ｂ）Ｃｕ Ｃｕは、素地を強化し、強度を向上させる作用がある
が、その含有量が１重量％未満ではその効果が十分でな
く、一方、４重量％を越えると材料の脆化を促進させる
ようになることから、Ｃｕの含有量は、１〜４重量％に
定めた。Ｃｕの含有量の一層好ましい範囲は２〜３重量
％である。(B) Cu Cu has the effect of strengthening the base material and improving the strength, but if its content is less than 1% by weight, its effect is not sufficient, while if it exceeds 4% by weight, the material Since the embrittlement is promoted, the content of Cu is set to 1 to 4% by weight. A more preferable range of the Cu content is 2-3% by weight.
【００１０】（ｃ）Ｍｏ Ｍｏは、耐摩耗性、強度、耐熱性を向上させる作用があ
るが、その含有量が０．５重量％未満では所望の効果が
得られず、一方、４重量％を越えると炭化物の粒状かが
困難であり、また、原料として用いるＦｅ−Ｍｏ粉末の
圧縮性および成形性が低下する様になるところから、そ
の含有量を０．５〜４重量％に定めた。Ｍｏの含有量の
一層好ましい範囲は０．８〜３．５重量％である。(C) Mo Mo has the effect of improving wear resistance, strength, and heat resistance, but if its content is less than 0.5% by weight, the desired effect cannot be obtained, while 4% by weight If it exceeds, it becomes difficult to granulate the carbide, and the compressibility and moldability of the Fe-Mo powder used as a raw material deteriorates. Therefore, the content was set to 0.5 to 4% by weight. . A more preferable range of the Mo content is 0.8 to 3.5% by weight.
【００１１】（ｂ）Ｃ Ｃは、素地に固溶して強度を向上させる効果があるほ
か、Ｍｏと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重量％未満では効果が十
分でなく、一方、０．９重量％を越えて含有すると材料
を脆化を促進させるので好ましくない。したがって、Ｃ
の含有量は、０．５〜０．９重量％に定めた。Ｃの含有
量の一層好ましい範囲は０．６〜０．８重量％である。(B) C C has the effect of forming a solid solution in the base material to improve the strength, and the effect of forming carbides with Mo to improve the wear resistance, but the content of C is 0.5. If it is less than wt%, the effect is not sufficient, while if it exceeds 0.9 wt%, embrittlement of the material is promoted, which is not preferable. Therefore, C
The content of was determined to be 0.5 to 0.9% by weight. A more preferable range of the C content is 0.6 to 0.8% by weight.
【００１２】Ｂ：組織 この発明の鉄基焼結合金は、マルテンサイト素地中に分
散する炭化物の粒径が強度に多大な影響を及ぼし、その
平均粒径が０．１μｍ未満では耐摩耗性向上効果が小さ
いので好ましくなく、一方、粒状炭化物の平均粒径が５
μｍを越えると、強度が低下するので好ましくない。し
たがって、粒状炭化物の平均粒径は、０．１〜５μｍに
限定した。粒状炭化物の平均粒径の一層好ましい範囲
は、０．５〜３．５μｍである。B: Microstructure In the iron-based sintered alloy of the present invention, the grain size of the carbide dispersed in the martensite matrix has a great influence on the strength, and if the average grain size is less than 0.1 μm, the wear resistance is improved. It is not preferable because the effect is small. On the other hand, the average particle size of the granular carbides is 5
When it exceeds μm, the strength is lowered, which is not preferable. Therefore, the average particle size of the granular carbide is limited to 0.1 to 5 μm. A more preferable range of the average particle size of the granular carbide is 0.5 to 3.5 μm.
【００１３】[0013]
実施例 原料粉末として、平均粒径：４７μｍのＦｅ−Ｍｏ粉
末、平均粒径：３μｍのＮｉ粉末、平均粒径：３７μｍ
のＣｕ粉末および平均粒径：１８μｍの黒鉛粉末を用意
し、これら原料粉末を金型成形時の潤滑剤であるステア
リン酸亜鉛粉末とともにダブルコーンミキサーで混合
し、プレス成形して９０ｍｍ×１３ｍｍ×１０ｍｍの寸
法および圧粉密度：７．０ｇ／ｃｃの圧粉体を作製し、
この圧粉体をＮ2 −５％Ｈ2 の雰囲気中、温度：１１２
０℃、３０分保持の条件で焼結したのち室温まで炉冷
し、表１に示される成分組成を有する焼結体Ａ〜Ｋを作
製した。Example As the raw material powder, Fe-Mo powder having an average particle size of 47 μm, Ni powder having an average particle size of 3 μm, and average particle size of 37 μm
Cu powder and graphite powder having an average particle size of 18 μm are prepared, and these raw material powders are mixed with a zinc stearate powder which is a lubricant at the time of mold molding in a double cone mixer, and press-molded to 90 mm × 13 mm × 10 mm. And the green compact density: 7.0g / cc
This green compact was heated at a temperature of 112 in an atmosphere of N 2 -5% H 2.
After sintering at 0 ° C. for 30 minutes, the furnace was cooled to room temperature, and sintered bodies A to K having the component compositions shown in Table 1 were prepared.
【００１４】[0014]
【表１】 [Table 1]
【００１５】つぎに、これら焼結体Ａ〜Ｋを、焼結雰囲
気と同じＮ2 −５％Ｈ2 の雰囲気中、表２に示されるオ
ーステナイト直上温度に表２に示される時間保持したの
ち、ただちに油焼入れし、つづいて１８０℃、６０分保
持の条件で焼戻しすることにより、マルテンサイト素地
中に表２に示される平均粒径の粒状化炭化物が分散した
組織を有する本発明鉄基焼結合金１〜１１を作製した。
この本発明鉄基焼結合金１〜１１を機械加工して試験片
を作製し、この試験片を用いて引張速度：１ｍｍ／ｍｉ
ｎで引張り試験を行うことにより引張り強さを測定し、
さらにノッチ無しシャルピー試験片を用いてシャルピー
衝撃試験を行うことによりシャルピー衝撃エネルギーを
測定し、それらの測定結果を表２に示した。Next, after holding these sintered bodies A to K in the same N 2 -5% H 2 atmosphere as the sintering atmosphere at the temperature just above the austenite shown in Table 2 for the time shown in Table 2, Immediately oil quenching, followed by tempering under the conditions of holding at 180 ° C. for 60 minutes, the iron-based firing bond of the present invention having a structure in which a granular carbide having an average particle size shown in Table 2 is dispersed in the martensite matrix. Gold 1 to 11 were produced.
The iron-based sintered alloys 1 to 11 of the present invention were machined to produce a test piece, and the test piece was used to pull at a speed of 1 mm / mi.
The tensile strength is measured by performing a tensile test with n.
Further, the Charpy impact energy was measured by performing a Charpy impact test using a notched Charpy test piece, and the measurement results are shown in Table 2.
【００１６】この発明の鉄基焼結合金の組織を一層理解
しやすくするために、本発明鉄基焼結合金１の組織を金
属顕微鏡により観察し、その写生図を図１に示した。図
１の写生図から、本発明鉄基焼結合金１にはマルテンサ
イト素地中に微細な炭化物粒が分散した組織を有するこ
とが分かる。In order to make the structure of the iron-based sintered alloy of the present invention easier to understand, the structure of the iron-based sintered alloy 1 of the present invention was observed with a metallurgical microscope, and its sketch is shown in FIG. From the drawing of FIG. 1, it can be seen that the iron-based sintered alloy 1 of the present invention has a structure in which fine carbide grains are dispersed in the martensite matrix.
【００１７】[0017]
【表２】 [Table 2]
【００１８】従来例 さらに比較のために、実施例で作製した表１の焼結体Ａ
〜Ｋを、オーステナイト直上温度に加熱保持して炭化物
粒状化処理を行うことなく、完全オーステナイト化温度
に加熱保持したのち油焼き入れし、ついで温度：１８０
℃に６０分間の低温焼戻し処理して表３に示される従来
鉄基焼結合金１〜１１を作製した。この従来鉄基焼結合
金１〜１１を機械加工して試験片を作製し、この試験片
を用いて実施例と同様にして引張り強さおよびシャルピ
ー衝撃エネルギーを測定し、それらの測定結果を表３に
示した。さらに、従来鉄基焼結合金１の組織を金属顕微
鏡により観察し、その写生図を図２に示した。図２の写
生図から、従来鉄基焼結合金１はマルテンサイト組織を
有することが分かる。Conventional Example Further, for comparison, the sintered body A of Table 1 produced in the example.
-K is heated and maintained at a temperature just above austenite and is not heated to be completely austenitized, and then oil-quenched, and then the temperature is 180.
A low temperature tempering treatment was performed at 60 ° C. for 60 minutes to produce the conventional iron-based sintered alloys 1 to 11 shown in Table 3. The conventional iron-based sintered alloys 1 to 11 were machined to prepare a test piece, and the test piece was used to measure the tensile strength and the Charpy impact energy in the same manner as in the example, and the measurement results are shown in a table. Shown in 3. Furthermore, the structure of the conventional iron-based sintered alloy 1 was observed with a metallurgical microscope, and its sketch is shown in FIG. From the drawing of FIG. 2, it can be seen that the conventional iron-based sintered alloy 1 has a martensite structure.
【００１９】[0019]
【表３】 [Table 3]
【００２０】[0020]
【発明の効果】表１〜表３に示した結果から、本発明鉄
基焼結合金１と従来鉄基焼結合金１を比較すると、本発
明鉄基焼結合金１と従来鉄基焼結合金１とは成分組成は
同じであっても組織が異なることによって一段と優れた
引張り強さおよびシャルピー衝撃エネルギー値を有する
ようになることが分かる。同様にして、本発明鉄基焼結
合金２〜１１と従来鉄基焼結合金２〜１１をそれぞれ比
較すると、本発明鉄基焼結合金２〜１１と従来鉄基焼結
合金２〜１１とはそれぞれ成分組成は同じであっても組
織が異なることによって一段と優れた引張り強さおよび
シャルピー衝撃エネルギー値を有するようになることが
分かる。From the results shown in Tables 1 to 3, when comparing the iron-based sintered alloy 1 of the present invention and the conventional iron-based sintered alloy 1, the iron-based sintered alloy 1 of the present invention and the conventional iron-based sintered bond are compared. It can be seen that even if the composition of the composition is the same as that of gold 1, the composition has a different structure, so that the composition has much more excellent tensile strength and Charpy impact energy value. Similarly, comparing the iron-based sintered alloys 2 to 11 of the present invention and the conventional iron-based sintered alloys 2 to 11 with the iron-based sintered alloys 2 to 11 of the present invention and the conventional iron-based sintered alloys 2 to 11, respectively. It can be seen that, even though the respective component compositions are the same, due to the different structures, the tensile strength and Charpy impact energy value become more excellent.
【００２１】上述のように、この発明の鉄基焼結合金
は、引張り強さおよびシャルピー衝撃値が優れているの
で、機械装置の部品の材料として、優れた性能を長期に
わたって発揮することができ、工業上優れた効果をもた
らすものである。As described above, since the iron-based sintered alloy of the present invention is excellent in tensile strength and Charpy impact value, it can exhibit excellent performance as a material of parts of machinery for a long period of time. , Which brings an excellent industrial effect.
【図１】この発明の鉄基焼結合金の金属顕微鏡組織の写
生図である。FIG. 1 is a drawing of a metallographic structure of an iron-based sintered alloy of the present invention.
【図２】従来の鉄基焼結合金の金属顕微鏡組織の写生図
である。FIG. 2 is a drawing of a metallographic structure of a conventional iron-based sintered alloy.
Claims (3)
重量％、Ｃ：０．５〜０．９重量％を含有し、残りがＦ
ｅおよび不可避不純物からなる組成、並びにマルテンサ
イト素地中に平均粒径：０．１〜５μｍの粒状炭化物が
分散した組織を有することを特徴とする高強度鉄基焼結
合金。1. Ni: 1 to 4% by weight, Mo: 0.5 to 4
% By weight, C: 0.5 to 0.9% by weight, the balance being F
A high-strength iron-based sintered alloy having a composition comprising e and unavoidable impurities, and a structure in which granular carbide having an average particle diameter of 0.1 to 5 μm is dispersed in a martensite matrix.
重量％、Ｃ：０．５〜０．９重量％を含有し、残りがＦ
ｅおよび不可避不純物からなる組成、並びにマルテンサ
イト素地中に平均粒径：０．１〜５μｍの粒状炭化物が
分散した組織を有することを特徴とする高強度鉄基焼結
合金。2. Cu: 1 to 4% by weight, Mo: 0.5 to 4
% By weight, C: 0.5 to 0.9% by weight, the balance being F
A high-strength iron-based sintered alloy having a composition comprising e and unavoidable impurities, and a structure in which granular carbide having an average particle diameter of 0.1 to 5 μm is dispersed in a martensite matrix.
％、Ｍｏ：０．５〜４重量％、Ｃ：０．５〜０．９重量
％を含有し、残りがＦｅおよび不可避不純物からなる組
成、並びにマルテンサイト素地中に平均粒径：０．１〜
５μｍの粒状炭化物が分散した組織を有することを特徴
とする高強度鉄基焼結合金。3. Ni: 1 to 4% by weight, Cu: 1 to 4% by weight, Mo: 0.5 to 4% by weight, C: 0.5 to 0.9% by weight, the balance being Fe and Composition consisting of inevitable impurities and average particle size in the martensite matrix: 0.1
A high-strength iron-based sintered alloy having a structure in which granular carbides of 5 μm are dispersed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31537495A JPH09157805A (en) | 1995-12-04 | 1995-12-04 | High strength iron base sintered alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31537495A JPH09157805A (en) | 1995-12-04 | 1995-12-04 | High strength iron base sintered alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09157805A true JPH09157805A (en) | 1997-06-17 |
Family
ID=18064643
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP31537495A Withdrawn JPH09157805A (en) | 1995-12-04 | 1995-12-04 | High strength iron base sintered alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09157805A (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2390372A (en) * | 2002-06-03 | 2004-01-07 | Tsubakimoto Chain Co | Sintered sprocket and manufacturing method |
| GB2395762A (en) * | 2002-11-29 | 2004-06-02 | Tsubakimoto Chain Co | Ratchet type tensioner having a pawl composed of high-density sintered alloy |
| GB2398853A (en) * | 2003-02-28 | 2004-09-01 | Tsubakimoto Chain Co | Ratchet type tensioner pawl |
| CN100338373C (en) * | 2003-07-22 | 2007-09-19 | 日产自动车株式会社 | Sintered chain gear for silent chain and producing method thereof |
| CN102990066A (en) * | 2012-11-25 | 2013-03-27 | 安徽普源分离机械制造有限公司 | Powder metallurgy forming and preparation method of valve rod of diaphragm valve |
| CN103264158A (en) * | 2013-05-27 | 2013-08-28 | 无锡市恒特力金属制品有限公司 | Powder metallurgy material for rotor of oil pump of gearbox |
| RU2570141C2 (en) * | 2013-10-21 | 2015-12-10 | Федеральное Государственное Бюджетное Образовательное Учреждение Высшего Профессионального Образования "Дагестанский Государственный Технический Университет" (Дгту) | Powder sparingly alloyed material based on iron to produce surface hardened wear-resistant parts |
-
1995
- 1995-12-04 JP JP31537495A patent/JPH09157805A/en not_active Withdrawn
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2390372A (en) * | 2002-06-03 | 2004-01-07 | Tsubakimoto Chain Co | Sintered sprocket and manufacturing method |
| GB2390372B (en) * | 2002-06-03 | 2005-06-08 | Tsubakimoto Chain Co | Sintered sprocket |
| GB2395762A (en) * | 2002-11-29 | 2004-06-02 | Tsubakimoto Chain Co | Ratchet type tensioner having a pawl composed of high-density sintered alloy |
| GB2395762B (en) * | 2002-11-29 | 2006-06-14 | Tsubakimoto Chain Co | Ratchet type tensioner |
| GB2398853A (en) * | 2003-02-28 | 2004-09-01 | Tsubakimoto Chain Co | Ratchet type tensioner pawl |
| GB2398853B (en) * | 2003-02-28 | 2005-10-12 | Tsubakimoto Chain Co | Ratchet type tensioner |
| CN100338373C (en) * | 2003-07-22 | 2007-09-19 | 日产自动车株式会社 | Sintered chain gear for silent chain and producing method thereof |
| CN102990066A (en) * | 2012-11-25 | 2013-03-27 | 安徽普源分离机械制造有限公司 | Powder metallurgy forming and preparation method of valve rod of diaphragm valve |
| CN103264158A (en) * | 2013-05-27 | 2013-08-28 | 无锡市恒特力金属制品有限公司 | Powder metallurgy material for rotor of oil pump of gearbox |
| RU2570141C2 (en) * | 2013-10-21 | 2015-12-10 | Федеральное Государственное Бюджетное Образовательное Учреждение Высшего Профессионального Образования "Дагестанский Государственный Технический Университет" (Дгту) | Powder sparingly alloyed material based on iron to produce surface hardened wear-resistant parts |
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