JP2010014023A - Governor weight and method for manufacturing the same - Google Patents
Governor weight and method for manufacturing the same Download PDFInfo
- Publication number
- JP2010014023A JP2010014023A JP2008174734A JP2008174734A JP2010014023A JP 2010014023 A JP2010014023 A JP 2010014023A JP 2008174734 A JP2008174734 A JP 2008174734A JP 2008174734 A JP2008174734 A JP 2008174734A JP 2010014023 A JP2010014023 A JP 2010014023A
- Authority
- JP
- Japan
- Prior art keywords
- amount
- mass
- powder
- governor
- governor weight
- 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.)
- Granted
Links
Images
Abstract
Description
本発明は、ディーゼルエンジンの燃料噴射ポンプの燃料噴射量を調節する調量機構を操作するガバナ装置に用いられるガバナウエイトおよびその製造方法に関する。 The present invention relates to a governor weight used in a governor device for operating a metering mechanism for adjusting a fuel injection amount of a fuel injection pump of a diesel engine, and a method for manufacturing the same.
ディーゼルエンジンは、燃料噴射量を調節することにより出力が制御される。したがって、アクセル開度が一定の下では、エンジンの回転速度の上昇に伴い燃料噴射量を減少させる必要があり、この制御を行う装置がガバナ装置である。図１は、このようなガバナ装置の一例を示しており、符号１は、図において上下方向に延びるポンプ駆動用のガバナシャフトである。このガバナシャフト１の先端部（下端部）には、鍔状のガバナウエイトホルダ２が固着されている。そしてこのガバナウエイトホルダ２の下面には、ピン３を介して、複数のガバナウエイト４が図１中矢印Ａ−Ｂ方向に揺動自在に支持されている。また、ガバナウエイトホルダ２の下方には、上端部に鍔部５ａが一体形成された円筒状のガバナスリーブ５が、ガバナウエイトホルダ２と同心状に、かつ軸方向に沿って移動可能に配設されている。
The output of the diesel engine is controlled by adjusting the fuel injection amount. Therefore, when the accelerator opening is constant, it is necessary to decrease the fuel injection amount as the engine speed increases, and the device that performs this control is the governor device. FIG. 1 shows an example of such a governor device.
ガバナウエイト４の揺動基端部には、内側に延びる爪部４ａが一体形成されており、この爪部４ａに、ガバナスリーブ５の鍔部５ａが摺動回転可能に係合している。ガバナスリーブ５の先端部には、ガバナレバー７の一端部に設けられたシフタ６が当接している。ガバナレバー７は、長手方向中間部が、レバー軸８によって矢印Ｃ−Ｄ方向に回転自在に支持されており、なおかつ、スプリング９の矢印Ｅ方向への引っ張り力によって矢印Ｄ方向への回転力が与えられている。ガバナレバー７の、シフタ６が設けられた側とは反対側の他端部は、ガバナリンク１０を介して、燃料噴射ポンプのコントロールラック１１に連結されている。
A
このガバナ装置においては、図２（中心線Ｏの左側が非作動状態、右側が作動状態）に示すように、ガバナシャフト１の回転速度が増すと、ガバナウエイト４が遠心力を受け、リンク３を中心に外側（Ｂ方向）に揺動する。このガバナウエイト４の揺動によりガバナスリーブ５がガバナウエイト４の爪部４ａにより押し下げられ、ガバナスリーブ５が下方に移動し、さらにこのガバナスリーブ６の動きにより、シフタ６の一端部が押し下げられる。この動作により、ガバナレバー７がスプリング９の引っ張り力に抗して図１のＣ方向に回転し、このガバナレバー７の回転動作がガバナリンク１０を介してコントロールラック１１に伝達されて、燃料噴射量が制御（減少）される。
In this governor device, as shown in FIG. 2 (the left side of the center line O is in an inoperative state and the right side is in an actuated state), the
さて、このようなガバナ装置に用いられるガバナウエイトやガバナスリーブは、粉末冶金法により製造される焼結部品が適用されているものがある（特許文献１）。粉末冶金法により製造される焼結部品は、原料粉末を、所望の形状の押型の型孔に充填し、その粉末を上下のパンチにより圧粉成形して成形体を得、次いでその成形体を焼結して原料粉末を相互に拡散させて結合させたものである。このような粉末冶金法による製品成形技術は、ニアネットシェイプに造形することができることに加え、一度押型を作製すれば同形状の製品を多量に生産可能であるという利点を有することから、各種作業用部品の製造に適用が進んでおり、複雑な形状を呈する上記ガバナウエイトの製造に好適な方法である。 Now, some governor weights and governor sleeves used in such governor apparatuses are applied with sintered parts manufactured by powder metallurgy (Patent Document 1). In sintered parts manufactured by powder metallurgy, raw material powder is filled into a mold cavity of a desired shape, and the powder is compacted by upper and lower punches to obtain a molded body. Sintering is performed by diffusing raw material powders to each other and bonding them. In addition to being able to form a near-net shape, this product molding technology by powder metallurgy has the advantage that once a stamping die is produced, it is possible to produce a large number of products of the same shape. This method is suitable for manufacturing the governor weight having a complicated shape.
図１および図２に示したガバナウエイト４の爪部４ａは、高速回転しながら揺動するといった２つの動作がいずれもガバナスリーブ５の鍔部５ａに対して摺動する状態で発生するため、高い耐摩耗性が要求される。すなわち、ガバナウエイト４の爪部４ａが摩耗するとガバナスリーブ５の移動量が減少し、コントロールラック１１の移動量が減少することとなる結果、適切な燃料噴射量の制御が果たせなくなる。このため、ガバナウエイト４には硬質クロムめっき処理が施されたものが適用されている。ところが、硬質クロムめっき処理はコストが高いことから、ガバナウエイトの製品単価が高くなってしまう。このため、硬質クロムめっき処理を施さなくても済むような耐摩耗性の高い焼結合金からなるガバナウエイトが望まれている。
Since the
また、特許文献１に記載のものは、耐摩耗性向上といった上記課題の解決策として、平均粒子径が１７０μｍ以下でビッカース硬さが１０００ＨＶ以上の硬質粒子（フェロクロム粒子）を３〜１１質量％含む鉄基焼結材によってガバナウエイトを構成することにより、硬質クロムめっき処理を行うことなく、摺動部品の耐摩耗性を高めるとともに、製造工程の簡略化を図ったものである。しかしながら、耐摩耗性向上が未だ十分なものではなく、より高い耐摩耗性を有するものが望まれている。
Moreover, the thing of
よって本発明は、高い耐摩耗性を有するとともに安価に製造することができる焼結合金からなるガバナウエイトおよびその製造方法を提供することを目的とする。 Therefore, an object of this invention is to provide the governor weight which consists of a sintered alloy which has high abrasion resistance and can be manufactured cheaply, and its manufacturing method.
本発明のガバナウエイトは、燃料噴射ポンプのガバナ装置に用いられるガバナウエイトであって、全体組成が、質量比で、Ｎｉ：１〜５％、Ｃｕ：０．５〜３％、Ｃｒ：０．６〜４％、Ｍｏ：０．６〜４％、Ｖ：０．２〜１．５％、Ｗ：０．６〜４％、Ｓｉ：０．０２〜０．５％、Ｃ：０．７〜１％、および残部がＦｅと不可避不純物からなるとともに、Ｎｉリッチのオーステナイト相が分散するマルテンサイト基地中に、Ｆｅ基合金基地中にＣｒ，Ｍｏ，Ｗ，Ｖの炭化物が群状に析出分散する硬質相が２０〜５０質量％分散する金属組織を呈する焼結合金からなることを特徴としている。 The governor weight of the present invention is a governor weight used in a governor device of a fuel injection pump, and the total composition is Ni: 1 to 5%, Cu: 0.5 to 3%, Cr: 0.00. 6-4%, Mo: 0.6-4%, V: 0.2-1.5%, W: 0.6-4%, Si: 0.02-0.5%, C: 0.7 ~ 1%, and the balance consists of Fe and inevitable impurities, and Ni, austenite phase is dispersed in the martensite matrix, and Cr, Mo, W, V carbides are precipitated and dispersed in groups in the Fe-based alloy matrix The hard phase is made of a sintered alloy exhibiting a metal structure in which 20 to 50% by mass is dispersed.
本発明によれば、優れた耐摩耗性を有するガバナウエイトを、硬質クロムめっき処理が不要であることから安価に製造することができるといった効果を奏する。 According to the present invention, there is an effect that a governor weight having excellent wear resistance can be manufactured at low cost since the hard chrome plating process is unnecessary.
本発明のガバナウエイトを構成する焼結合金は、図３の模式図に示すように、Ｆｅ−Ｎｉ−Ｃｕ−Ｃ系合金からなりＮｉリッチのオーステナイト相が分散するマルテンサイト基地中に、Ｆｅ−Ｃｒ−Ｍｏ−Ｗ−Ｖ系合金からなりＦｅ基合金基地中にＣｒ，Ｍｏ，Ｗ，Ｖの炭化物が群状に析出分散する硬質相が分散するものである。すなわち、上記特許文献１のように、微細な硬質粒子が基地中に均一に分散する場合には、基地の塑性流動を有効に抑制するためには多量の硬質粒子が必要となり、相手攻撃性が高まることとなるが、本発明のガバナウエイトを構成する焼結合金は、微細な硬質粒子が群としてスポット状に基地中に分散するため、群状に析出した硬質粒子が基地の塑性流動を有効に抑制するとともに、硬質相の分散しない基地部分が多いことから相手攻撃性も抑制されるという優れた効果を有するものである。
As shown in the schematic diagram of FIG. 3, the sintered alloy constituting the governor weight of the present invention is made of Fe—Ni—Cu—C-based alloy and a Fe—Ni—Cu—C-based alloy in which a Ni-rich austenite phase is dispersed. A hard phase in which carbides of Cr, Mo, W, and V are precipitated and dispersed in a group form is dispersed in a Fe-based alloy base made of a Cr—Mo—W—V alloy. That is, as in the above-mentioned
以下、本発明のガバナウエイトを構成する合金が含有する各元素や硬質相の含有量の根拠を説明する。
（１）Ｃｕ
基地を構成するＣｕは、Ｆｅ基地に固溶して基地強化に働くとともに、基地の焼き入れ性を向上させて基地の強度および耐摩耗性の向上に寄与する。ここで、全体組成中のＣｕ量が０．５質量％に満たないと基地強化の作用に乏しい。一方、５質量％を超えて与えると、過飽和なＣｕが軟質なＣｕ相として析出する結果、基地強度が著しく低下する。このため、全体組成中のＣｕ量を０．５〜３質量％とする。このＣｕはＦｅ基地への拡散の速度が高いこと、および鉄粉末に固溶させて与えると、鉄粉末の硬さが高くなり成形性が低下することから、全量を銅粉末の形態で付与する。このため、本発明のガバナウエイトの製造方法においては、原料粉末として、鉄粉に０．５〜３質量％の銅粉末を添加することとする。
Hereinafter, the basis of the content of each element and the hard phase contained in the alloy constituting the governor weight of the present invention will be described.
(1) Cu
Cu constituting the base is dissolved in the Fe base and works to strengthen the base, and improves the hardenability of the base and contributes to the improvement of the strength and wear resistance of the base. Here, if the amount of Cu in the entire composition is less than 0.5% by mass, the effect of strengthening the base is poor. On the other hand, if the content exceeds 5% by mass, supersaturated Cu is precipitated as a soft Cu phase, and as a result, the base strength is significantly reduced. For this reason, the amount of Cu in the whole composition is 0.5-3 mass%. Since this Cu has a high diffusion rate to the Fe base, and when dissolved in iron powder, the hardness of the iron powder increases and the formability decreases, so the entire amount is applied in the form of copper powder. . For this reason, in the manufacturing method of the governor weight of this invention, suppose that 0.5-3 mass% copper powder is added to iron powder as raw material powder.
（２）Ｎｉ
基地を構成するＮｉは、Ｆｅ基地に固溶して基地強化に働くとともに、基地の焼き入れ性を向上させて基地の強度および耐摩耗性の向上に寄与する。また、Ｎｉリッチのオーステナイト相を形成して、焼結合金の衝撃値を向上させるとともに、相手攻撃性の緩和する作用を有する。ここで、全体組成中のＮｉ量が１質量％に満たないと上記の効果が乏しくなる。一方、５質量％を超えて与えると、Ｎｉリッチのオーステナイト相の量が増大し、基地の強度が低下することとなる。このため、全体組成中のＮｉ量を１〜５質量％とする。このＮｉはＮｉリッチのオーステナイト相を形成するため、全量をニッケル粉末の形態で付与する。このため、本発明のガバナウエイトの製造方法においては、原料粉末として、鉄粉に１〜５質量％のニッケル粉末を添加することとする。
(2) Ni
Ni constituting the base dissolves in the Fe base and works to strengthen the base, and improves the hardenability of the base and contributes to improvement of the strength and wear resistance of the base. In addition, the Ni-rich austenite phase is formed, and the impact value of the sintered alloy is improved, and the opponent aggression is alleviated. Here, if the amount of Ni in the overall composition is less than 1% by mass, the above effect is poor. On the other hand, if the content exceeds 5% by mass, the amount of Ni-rich austenite phase increases and the strength of the base decreases. For this reason, the amount of Ni in the entire composition is set to 1 to 5% by mass. Since this Ni forms a Ni-rich austenite phase, the entire amount is applied in the form of nickel powder. For this reason, in the manufacturing method of the governor weight of this invention, suppose that 1-5 mass% nickel powder is added to iron powder as raw material powder.
（３）硬質相
Ｃｒ，Ｍｏ，ＷおよびＶは、硬質相中に金属炭化物として群状に析出して焼結合金の耐摩耗性の向上に寄与する。また、Ｃｒ，Ｍｏ，ＷおよびＶの金属炭化物を群状に析出させるため、Ｃｒ，Ｍｏ，ＷおよびＶは合金粉末の形態で付与される必要があるが、基地との固着性を考慮して硬質相の基地部分をＦｅとし、鉄合金粉末の形態で原料粉末に添加することとする。このような金属炭化物が群状に析出する硬質相は、２０質量％に満たないと耐摩耗性向上の効果が乏しくなる。一方、５０質量％を超えると硬質な鉄合金粉末の量が過多となる結果、原料粉末の成形性が著しく損なわれるともに、相手攻撃性が高くなる。このため、基地中に分散する硬質相の量を２０〜５０質量％とする。
(3) Hard phase Cr, Mo, W, and V precipitate in the form of metal carbides in the hard phase as a group, and contribute to improving the wear resistance of the sintered alloy. In addition, Cr, Mo, W, and V metal carbides are precipitated in groups, so Cr, Mo, W, and V need to be applied in the form of alloy powder. The base portion of the hard phase is Fe and is added to the raw material powder in the form of an iron alloy powder. If the hard phase in which such metal carbide precipitates in a group is less than 20% by mass, the effect of improving the wear resistance is poor. On the other hand, if it exceeds 50% by mass, the amount of the hard iron alloy powder becomes excessive. As a result, the formability of the raw material powder is remarkably impaired, and the opponent attack is increased. For this reason, the quantity of the hard phase disperse | distributed in a base shall be 20-50 mass%.
ここで鉄合金粉末中のＣｒが３質量％、Ｍｏが３質量％、Ｖが１質量％、Ｗが３質量％にそれぞれ満たないと、析出する金属炭化物の量が乏しくなり、耐摩耗性向上の効果が乏しくなる。一方、鉄合金粉末中のＣｒが８質量％、Ｍｏが８質量％、Ｖが３質量％、Ｗが８質量％をそれぞれ超えると、これらの元素を固溶する鉄合金粉末の硬さが増大する結果、原料粉末の成形性が著しく損なわれることとなる。このため、鉄合金粉末中のＣｒ量を３〜８質量％、Ｍｏ量を３〜８質量％、Ｖ量を１〜３質量％、Ｗ量を３〜８質量％とする。したがって、全体組成中のＣｒ量は０．６〜４質量％、Ｍｏ量は０．６〜４質量％、Ｖ量は０．２〜１．５質量％、Ｗ量は０．６〜４質量％となる。 Here, if the amount of Cr in the iron alloy powder is less than 3% by mass, Mo is 3% by mass, V is less than 1% by mass, and W is less than 3% by mass, the amount of precipitated metal carbide is reduced and the wear resistance is improved. The effect of becomes poor. On the other hand, if the Cr content in the iron alloy powder exceeds 8 mass%, Mo exceeds 8 mass%, V exceeds 3 mass%, and W exceeds 8 mass%, the hardness of the iron alloy powder that dissolves these elements increases. As a result, the formability of the raw material powder is significantly impaired. For this reason, the amount of Cr in the iron alloy powder is 3 to 8 mass%, the amount of Mo is 3 to 8 mass%, the amount of V is 1 to 3 mass%, and the amount of W is 3 to 8 mass%. Therefore, the Cr amount in the whole composition is 0.6 to 4% by mass, the Mo amount is 0.6 to 4% by mass, the V amount is 0.2 to 1.5% by mass, and the W amount is 0.6 to 4% by mass. %.
（４）Ｓｉ
鉄合金粉末には、酸化し易いＣｒを含むため鉄合金粉末の製造時に脱酸剤として使用されるＳｉを含有するが、このＳｉは、硬質相のＦｅ基地のＣを排出して上記の金属炭化物の析出を促進するとともに、硬質相のＦｅ基地を強化するという働きをする。鉄合金粉末中のＳｉ量が０．１質量％に満たないと上記の効果が乏しく、１質量％を超えると硬質相のＦｅ基地の脆化が著しくなる。このため、鉄合金粉末中のＳｉ量を０．１〜１質量％とする。したがって、全体組成中のＳｉ量は０．０２〜０．５質量％となる。
(4) Si
Since the iron alloy powder contains Cr that is easily oxidized, it contains Si that is used as a deoxidizer during the production of the iron alloy powder. While promoting the precipitation of carbides, it works to strengthen the Fe base of the hard phase. If the amount of Si in the iron alloy powder is less than 0.1% by mass, the above effect is poor, and if it exceeds 1% by mass, the Fe base of the hard phase becomes brittle. For this reason, the amount of Si in iron alloy powder shall be 0.1-1 mass%. Therefore, the amount of Si in the entire composition is 0.02 to 0.5% by mass.
（５）Ｃ
Ｃは、Ｆｅ基地に固溶して基地強化に働くとともに、Ｆｅとともにマルテンサイトを形成して基地の強度および耐摩耗性の向上に寄与する。また、Ｃは、上記のようにＣｒ，Ｍｏ，Ｗ，Ｖと炭化物を形成して金属炭化物が群状に析出する硬質相を形成し、焼結合金の耐摩耗性の向上に寄与する。ここで、全体組成中のＣ量が０．７質量％に満たないと基地強化および基地の耐摩耗性向上の作用に乏しくなるとともに、硬質相中に析出する金属炭化物の量が乏しくなって耐摩耗性向上の作用が乏しくなる。一方、１質量％を超えて与えると、基地のマルテンサイトが硬くなり過ぎたり、硬質相中に析出する金属炭化物の量が多くなり過ぎたりして、相手攻撃性が著しく増大するとともに、基地が脆く摩耗し易くなる。このため、全体組成中のＣ量を０．７〜１質量％とする。
(5) C
C dissolves in the Fe base and works to strengthen the base, and also forms martensite with Fe and contributes to the improvement of the strength and wear resistance of the base. In addition, C forms carbides with Cr, Mo, W, and V as described above to form a hard phase in which metal carbides precipitate in groups, and contributes to improvement in wear resistance of the sintered alloy. Here, if the amount of C in the entire composition is less than 0.7% by mass, the effect of strengthening the base and improving the wear resistance of the base becomes poor, and the amount of metal carbides precipitated in the hard phase becomes poor and the resistance is increased. The effect of improving wear is poor. On the other hand, if the amount exceeds 1% by mass, the base martensite becomes too hard, or the amount of metal carbides precipitated in the hard phase increases too much. Brittle and easy to wear. For this reason, C amount in the whole composition shall be 0.7-1 mass%.
このＣは、鉄粉末に固溶して与えると、鉄合金粉末の硬さが高くなり成形性が低下することとなる。しかしながら、全量を黒鉛粉末の形態で付与すると、原料粉末の流動性や成形性が低下するとともに、偏析が生じ易くなることから得策ではない。一方、Ｃの全量を熱処理時の浸炭性ガス雰囲気により供給しようとすると、浸炭時間が長くなることから生産が低下して製造コストが増加することとなる。このため、Ｃは、一部を黒鉛粉末の形態で原料粉末に添加するとともに、不足分のＣを熱処理時の浸炭性ガス雰囲気により供給することとした。 When this C is given as a solid solution in the iron powder, the hardness of the iron alloy powder is increased and the formability is lowered. However, if the total amount is applied in the form of graphite powder, the fluidity and formability of the raw material powder are lowered, and segregation is likely to occur, which is not a good idea. On the other hand, if an attempt is made to supply the entire amount of C in the carburizing gas atmosphere at the time of heat treatment, the carburizing time becomes longer, so the production is reduced and the manufacturing cost is increased. Therefore, a part of C is added to the raw material powder in the form of graphite powder, and a shortage of C is supplied in a carburizing gas atmosphere during heat treatment.
また、硬質相を形成するための鉄合金粉末中においては、鉄合金粉末中にＣｒ，Ｍｏ，Ｗ，Ｖを固溶していることから鉄合金粉末の硬さが著しく増大する。そこで、鉄合金粉末中にＣを固溶させて鉄合金粉末中にＣｒ，Ｍｏ，Ｗ，Ｖの金属炭化物を析出させることにより、鉄合金粉末の基地中に固溶されるＣｒ，Ｍｏ，Ｗ，Ｖの量を低減して鉄合金粉末の硬さを低減することができる。したがって、鉄合金粉末の組成において０．８〜１．４質量％に相当する量（全体組成中のＣ量で０．１６〜０．５６質量％）のＣを鉄合金粉末に固溶させて与える必要がある。以上より、Ｃは、黒鉛粉末の形態で原料粉末に０．３〜１質量％添加するとともに、鉄合金粉末の組成において０．８〜１．４質量％に相当するＣ量を鉄合金粉末に固溶させて与え、不足分のＣ量を浸炭性ガス雰囲気により与えることとした。 Further, in the iron alloy powder for forming the hard phase, the hardness of the iron alloy powder is remarkably increased because Cr, Mo, W, V are dissolved in the iron alloy powder. Therefore, by dissolving C in the iron alloy powder and precipitating Cr, Mo, W, V metal carbides in the iron alloy powder, Cr, Mo, W dissolved in the base of the iron alloy powder. , V can be reduced to reduce the hardness of the iron alloy powder. Therefore, in the composition of the iron alloy powder, an amount of C corresponding to 0.8 to 1.4% by mass (0.16 to 0.56% by mass in the total composition) is dissolved in the iron alloy powder. Need to give. From the above, C is added in an amount of 0.3 to 1% by mass to the raw material powder in the form of graphite powder, and the amount of C corresponding to 0.8 to 1.4% by mass in the composition of the iron alloy powder is added to the iron alloy powder. It was decided to give the solution in a solid solution, and to give the amount of C in a short amount in a carburizing gas atmosphere.
以上より、本発明のガバナウエイトは、全体組成が、質量比で、Ｎｉ：１〜５％、Ｃｕ：０．５〜３％、Ｃｒ：０．６〜４％、Ｍｏ：０．６〜４％、Ｖ：０．２〜１．５％、Ｗ：０．６〜４％、Ｓｉ：０．０２〜０．５％、Ｃ：０．７〜１％、および残部がＦｅと不可避不純物からなるとともに、Ｎｉリッチのオーステナイト相が分散するマルテンサイト基地中に、Ｆｅ基合金基地中にＣｒ，Ｍｏ，Ｗ，Ｖの炭化物が群状に析出分散する硬質相が２０〜５０質量％分散する金属組織を呈する焼結合金により構成したものとなる。ここで、硬質相の組成としては、質量比で、Ｃｒ：３〜８％、Ｍｏ：３〜８％、Ｖ：１〜３％、Ｗ：３〜８％、Ｓｉ：０．１〜１％を含むものとする。 From the above, the overall composition of the governor weight of the present invention is Ni: 1 to 5%, Cu: 0.5 to 3%, Cr: 0.6 to 4%, Mo: 0.6 to 4 in mass ratio. %, V: 0.2 to 1.5%, W: 0.6 to 4%, Si: 0.02 to 0.5%, C: 0.7 to 1%, and the balance from Fe and inevitable impurities In addition, in the martensite matrix in which the Ni-rich austenite phase is dispersed, the hard phase in which the carbides of Cr, Mo, W, and V are precipitated and dispersed in a group form in the Fe-based alloy matrix is dispersed in 20 to 50% by mass. It is constituted by a sintered alloy exhibiting a structure. Here, the composition of the hard phase is, by mass ratio, Cr: 3-8%, Mo: 3-8%, V: 1-3%, W: 3-8%, Si: 0.1-1% Shall be included.
また、本発明のガバナウエイトの原料粉末は、鉄粉に、組成が、質量比で、Ｃｒ：３〜８％、Ｍｏ：３〜８％、Ｖ：１〜３％、Ｗ：３〜８％、Ｓｉ：０．１〜１％、Ｃ：０．８〜１．４％、および残部がＦｅと不可避不純物からなる鉄合金粉末を２０〜４０質量％と、ニッケル粉末を１〜５質量％と、銅粉末を０．５〜３質量％と、黒鉛粉末を０．３〜１質量％とを添加し、混合したものとする。 Moreover, the raw material powder of the governor weight of the present invention is composed of iron powder in a mass ratio of Cr: 3 to 8%, Mo: 3 to 8%, V: 1 to 3%, W: 3 to 8%. , Si: 0.1 to 1%, C: 0.8 to 1.4%, and iron alloy powder composed of Fe and inevitable impurities in the balance, 20 to 40% by mass, and nickel powder, 1 to 5% by mass In addition, 0.5 to 3% by mass of copper powder and 0.3 to 1% by mass of graphite powder are added and mixed.
上記の原料粉末は、通常の粉末冶金法で製造される焼結部品と同様に、ガバナウエイトの形状を有する押型の型孔に充填され、上下のパンチにより、成形体密度６．８〜７．２Ｍｇ／ｍ３に圧粉成形されてガバナウエイト形状の成形体とされる。次いで、得られた成形体は１０５０〜１２００℃で焼結され、原料粉末が相互に拡散させられ、結合させられる。このようにして得られたガバナウエイト形状の焼結体は、カーボンポテンシャル（Ｃｐ値）が０．７〜１．１の浸炭性ガス雰囲気中で８００〜１０００℃に加熱され、浸炭された後、油中に投入されて焼き入れされる。さらに、焼き入れされたガバナウエイトは、１６０〜２００℃に加熱されて焼き戻される。このようにして作製されたガバナウエイトは、上記の金属組織を呈するとともに、密度比が８５〜９５％（気孔率が５〜１５％）となり、この気孔に油が保持され、良好な耐摩耗性を示す。 The raw material powder is filled in a die hole of a die having a shape of a governor weight in the same manner as a sintered part manufactured by a normal powder metallurgy method, and a green body density of 6.8 to 7. It is compacted to 2Mg / m 3 to form a governor-weight shaped product. Subsequently, the obtained molded body is sintered at 1050 to 1200 ° C., and the raw material powders are diffused and bonded to each other. The governor-weight shaped sintered body thus obtained was heated to 800 to 1000 ° C. in a carburizing gas atmosphere having a carbon potential (Cp value) of 0.7 to 1.1 and carburized. It is put into oil and quenched. Further, the quenched governor weight is heated to 160 to 200 ° C. and tempered. The governor weight thus produced exhibits the above-described metal structure and a density ratio of 85 to 95% (porosity of 5 to 15%), oil is retained in the pores, and good wear resistance. Indicates.
本発明のガバナウエイトの製造方法は上記過程に基づくもので、上記の原料粉末を、所望の形状に圧粉成形し、次いで、得られた成形体を焼結し、次いで、得られた焼結体を浸炭焼き入れした後、焼き戻しを行うことを特徴としている。 The manufacturing method of the governor weight of the present invention is based on the above process, and the above raw material powder is compacted into a desired shape, and then the obtained molded body is sintered, and then the obtained sintered product is sintered. It is characterized by tempering after carburizing and quenching the body.
本発明のガバナウエイトは、特に、摺動する相手部材であるガバナスリーブとして、全体組成が、質量比で、Ｎｉ：２〜３％、Ｍｎ：０．１〜１％、Ｃ：０．２〜０．５％、および残部がＦｅと不可避不純物からなる焼結合金からなるものを用いた場合、従来の硬質クロムめっきを施したものよりも優れた耐摩耗性を示すとともに、相手攻撃性が小さくなるため、好適である。 In particular, the governor weight of the present invention, as a governor sleeve which is a sliding counterpart member, has an overall composition of Ni: 2-3%, Mn: 0.1-1%, C: 0.2- When using a sintered alloy consisting of 0.5% and the balance of Fe and inevitable impurities, the wear resistance is superior to that of conventional hard chrome plating, and the opponent attack is small. Therefore, it is preferable.
次いで、本発明の実施例を説明して本発明の効果を実証する。
［第１実施例］
鉄粉末、ニッケル粉末、銅粉末、黒鉛粉末、および組成が、質量比で、Ｃｒ：４．２％、Ｍｏ：５％、Ｗ：６％、Ｖ：１．８％、Ｓｉ：０．６％、Ｃ：１．１％であり残部がＦｅと不可避不純物からなる鉄合金粉末を用意した。これらの粉末を用いて、表１に示す配合比で鉄合金粉末の添加量を変えて添加、混合し、原料粉末を得た。次に、これら原料粉末を、成形圧力８３０ＭＰａで外径７．９８ｍｍ、高さ２０ｍｍの柱体形状に圧粉成形し、得られた成形体を、ブタン変性ガス雰囲気中において１１２０℃で焼結し、焼結体を得た。次に、得られた焼結体を、Ｃｐ値が０．９の浸炭性ガス雰囲気中において８５０℃に加熱した後、油中に焼き入れし、１８０℃で焼き戻して、表１に示す試料番号０２〜０８の柱体試料（ピン）を作製した。また、従来例として、焼き戻し後に硬質クロムめっき処理を施したものを試料番号０１として作製した。
Next, examples of the present invention will be described to demonstrate the effects of the present invention.
[First embodiment]
Iron powder, nickel powder, copper powder, graphite powder, and composition are, by mass ratio, Cr: 4.2%, Mo: 5%, W: 6%, V: 1.8%, Si: 0.6% , C: 1.1%, and an iron alloy powder comprising the balance Fe and inevitable impurities was prepared. Using these powders, the addition ratio of the iron alloy powder was changed and added and mixed at the compounding ratio shown in Table 1 to obtain a raw material powder. Next, these raw material powders are compacted into a columnar shape having an outer diameter of 7.98 mm and a height of 20 mm at a molding pressure of 830 MPa, and the obtained compact is sintered at 1120 ° C. in a butane-modified gas atmosphere. A sintered body was obtained. Next, the obtained sintered body was heated to 850 ° C. in a carburizing gas atmosphere having a Cp value of 0.9, then quenched in oil, tempered at 180 ° C., and the samples shown in Table 1 Column body samples (pins) numbered 02 to 08 were prepared. In addition, as a conventional example, a sample obtained by applying hard chrome plating after tempering was prepared as sample number 01.
また、摺動の相手材となるディスク試料を、以下のようにして作製した。組成が、質量比で、Ｎｉ：２．６％、Ｍｎ：０．５％であり、残部がＦｅと不可避不純物からなる鉄合金粉末に、黒鉛粉末を０．３質量％添加し混合した原料粉末を、成形圧力７００ＭＰａでφ４００ｍｍ、高さ５ｍｍの円板形状に圧粉成形し、得られた成形体を、ブタン変性ガス雰囲気中において１１２０℃で焼結して得た。得られた焼結体を、Ｃｐ値が０．９の浸炭性ガス雰囲気中において８５０℃に加熱した後、油中に焼き入れし、１８０℃で焼き戻して相手材となるディスク試料を作製した。 Further, a disk sample as a sliding counterpart was produced as follows. Raw material powder in which 0.3% by mass of graphite powder is added to and mixed with an iron alloy powder having a composition by mass ratio of Ni: 2.6% and Mn: 0.5% and the balance being Fe and inevitable impurities. Was molded into a disc shape having a molding pressure of 700 MPa and a diameter of 400 mm and a height of 5 mm, and the obtained molded body was obtained by sintering at 1120 ° C. in a butane-modified gas atmosphere. The obtained sintered body was heated to 850 ° C. in a carburizing gas atmosphere having a Cp value of 0.9, then quenched in oil and tempered at 180 ° C. to produce a disk sample as a counterpart material. .
各柱体試料２個をピンとし、一方、上記ディスク試料をピンの摺動相手材とし、荷重５ｋｇｆ／ｃｍ２のもと、周速１５０ｍ／分で６０分間摺動させて、ピン・オン・ディスク摩擦摩耗試験を行い、試験後の摩耗量を測定した。このときの試験結果を、表１に併記する。なお、ピン摩耗量は２個のピンの平均値である。 Two columnar samples are used as pins, while the above disk sample is used as a sliding member for the pins, and is slid for 60 minutes at a peripheral speed of 150 m / min under a load of 5 kgf / cm 2. A disc frictional wear test was performed, and the amount of wear after the test was measured. The test results at this time are also shown in Table 1. The pin wear amount is an average value of two pins.
表１の試料番号０１の試料は、鉄合金粉末が添加されておらず硬質相が分散しないものであり、かつ硬質クロムめっきを施したものであるといった点で、本発明のものとは異なる従来例である。この試料番号０１の試料は、合計摩耗量が３１μｍであるが、以下の実施例においては、試料番号０１の従来例よりも合計摩耗量が少ないものを目標とし、この目標を達成したものについて表の備考欄に“発明例”と記す。また、試料番号０１の従来例よりも合計摩耗量が多いものを本発明外のものとし、表の備考欄に“比較例”と記す。 The sample of sample number 01 in Table 1 is different from that of the present invention in that the iron alloy powder is not added, the hard phase is not dispersed, and a hard chromium plating is applied. It is an example. The sample No. 01 has a total wear amount of 31 μm. However, in the following examples, a sample having a total wear amount smaller than that of the conventional example No. 01 is set as a target, and a table showing the achievement of this target is shown below. In the remarks column of “Invention example”. Further, a sample having a total wear amount larger than that of the conventional example of Sample No. 01 is regarded as one outside the present invention, and “Comparative Example” is described in the remarks column of the table.
表１より、原料粉末への鉄合金粉末の添加量（焼結合金基地中の硬質粒子の分散量）の影響を調べることができる。すなわち、鉄合金粉末を添加せず、硬質クロムめっきを施さない試料番号０２の試料は、合計摩耗量が６２μｍと大きい値を示している。また、鉄合金粉末を１０質量％添加すると硬質相により焼結合金基地の流動が抑制され、ピン摩耗量が６割程度低減できるものの、まだ、硬質相の効果が乏しく、目標（３０μｍ以下）は達成できていない。しかしながら、鉄合金粉末の添加量が２０〜５０質量％の試料番号０３〜０７の試料では、硬質相の効果が発揮されて、ピン摩耗量が０．５〜６．５μｍと小さい値に抑制され、目標（合計摩耗量３０μｍ以下）が達成されている。 From Table 1, the influence of the amount of iron alloy powder added to the raw material powder (the amount of hard particles dispersed in the sintered alloy matrix) can be examined. That is, the sample No. 02 to which the iron alloy powder is not added and the hard chrome plating is not applied shows a large total wear amount of 62 μm. Moreover, when iron alloy powder is added at 10% by mass, the flow of the sintered alloy base is suppressed by the hard phase, and the amount of pin wear can be reduced by about 60%, but the effect of the hard phase is still poor, and the target (30 μm or less) is Not achieved. However, in the samples of sample numbers 03 to 07 where the added amount of iron alloy powder is 20 to 50% by mass, the effect of the hard phase is exhibited and the pin wear amount is suppressed to a small value of 0.5 to 6.5 μm. The target (total wear amount of 30 μm or less) has been achieved.
一方、鉄合金粉末の添加量が５０質量％を超える試料番号０８の試料は、硬質な鉄合金粉末が過多となって原料粉末の圧縮性が低下し、成形体密度の低下を招く結果、焼結体密度が低下し、焼結体の強度が低下することにより、ピン摩耗量が増大するとともに、ピンの摩耗粉が研磨粒子として作用してディスク摩耗量も増大している。この結果より、原料粉末への鉄合金粉末の添加量（焼結合金基地中の硬質粒子の分散量）は２０〜５０質量％とすべきことが確認された。 On the other hand, the sample of sample number 08 in which the added amount of the iron alloy powder exceeds 50% by mass is excessively hard iron alloy powder and the compressibility of the raw material powder is reduced, resulting in a decrease in the density of the compact. As the density of the sintered body decreases and the strength of the sintered body decreases, the amount of pin wear increases, and the pin wear powder acts as abrasive particles, increasing the amount of disk wear. From this result, it was confirmed that the addition amount of iron alloy powder to the raw material powder (dispersion amount of hard particles in the sintered alloy matrix) should be 20 to 50% by mass.
また、試料番号０３〜０７の試料について金属組織を観察したところ、Ｎｉリッチのオーステナイト相が分散するマルテンサイト基地中に、Ｆｅ基合金基地中にＣｒ，Ｍｏ，Ｗ，Ｖの炭化物が群状に析出分散する硬質相が分散していることが確認された。また、この硬質相は鉄合金粉末の添加量に応じて分散量が異なっており、鉄合金粉末により形成されたものであることが確認された。 Further, when the metal structures of the samples Nos. 03 to 07 were observed, the carbides of Cr, Mo, W, and V were grouped in the martensite matrix in which the Ni-rich austenite phase was dispersed and in the Fe-based alloy matrix. It was confirmed that the hard phase that precipitates and disperses is dispersed. Further, it was confirmed that the hard phase had a dispersion amount depending on the amount of iron alloy powder added, and was formed from the iron alloy powder.
［第２実施例］
上記第１実施例の鉄粉末、ニッケル粉末、銅粉末、鉄合金粉末および黒鉛粉末を用いるとともに、鉄合金粉末の添加量を３０質量％とし、表２に示すようにニッケル粉末の添加量を変えて配合、混合して、原料粉末を得た。次いで、これら原料粉末を、第１実施例と同様に成形、焼結、浸炭焼き入れ、焼き戻しを行って、試料番号０９〜１２の柱状試料（ピン）を作製した。これらの試料につき、第１実施例と同じ相手材を用い、かつ第１実施例と同じ条件でピン・オン・ディスク摩擦摩耗試験を行い、試験後の摩耗量を測定した。このときの試験結果を、表２に併記する。なお、表２には、第１実施例の試料番号０５の値を併せて示している。
[Second Embodiment]
While using the iron powder, nickel powder, copper powder, iron alloy powder and graphite powder of the first embodiment, the addition amount of the iron alloy powder is 30% by mass, and the addition amount of the nickel powder is changed as shown in Table 2. Were mixed and mixed to obtain a raw material powder. Subsequently, these raw material powders were molded, sintered, carburized and quenched, and tempered in the same manner as in the first example to prepare columnar samples (pins) of sample numbers 09 to 12. These samples were subjected to a pin-on-disk friction and wear test using the same mating material as in the first example and under the same conditions as in the first example, and the amount of wear after the test was measured. The test results at this time are also shown in Table 2. Table 2 also shows the value of sample number 05 of the first embodiment.
表２より、原料粉末へのニッケル粉末添加量（全体組成中のＮｉ量）の影響を調べることができる。すなわち、ニッケル粉末を添加せず、焼結合金基地にＮｉを含有しない試料番号０９の試料は、焼結合金基地の強化および焼き入れ性の改善がなされず、ピン摩耗量が増大している。一方、ニッケル粉末を１〜５質量％添加した試料番号１０，０５，１１の試料は、焼結合金基地の強化および焼き入れ性の改善がなされ、ピン摩耗量が半分以上抑制され、合計摩耗量も目標を達成している。 From Table 2, the influence of the amount of nickel powder added to the raw material powder (the amount of Ni in the overall composition) can be examined. That is, the sample No. 09 in which nickel powder is not added and Ni is not contained in the sintered alloy matrix does not strengthen the sintered alloy matrix and improve the hardenability, and the pin wear amount is increased. On the other hand, the samples Nos. 10, 05 and 11 to which 1 to 5% by mass of nickel powder is added have the sintered alloy base strengthened and improved hardenability, the pin wear amount is suppressed by more than half, and the total wear amount. Has also achieved the goal.
しかしながら、ニッケル粉末の添加量が５質量％を超える試料番号１２の試料では、ニッケル粉末の添加量が過多となって軟質なＮｉリッチのオーステナイト相が増加する結果、ピン摩耗量が増大している。また、焼結合金基地の焼き入れ性が向上し過ぎて焼結合金基地のマルテンサイトが硬く、かつ脆くなり、ディスクへの攻撃性が増加してディスク摩耗量も増大している。これらのことから、原料粉末へのニッケル粉末添加量（全体組成中のＮｉ量）は１〜５質量％とすべきことが確認された。 However, in the sample of Sample No. 12 in which the amount of nickel powder added exceeds 5% by mass, the amount of nickel powder added is excessive and the amount of soft Ni-rich austenite increases, resulting in an increase in pin wear. . Further, the hardenability of the sintered alloy base is improved too much, the martensite of the sintered alloy base becomes hard and brittle, the aggressiveness to the disk is increased, and the amount of wear of the disk is also increased. From these facts, it was confirmed that the amount of nickel powder added to the raw material powder (the amount of Ni in the overall composition) should be 1 to 5% by mass.
［第３実施例］
上記第１実施例の鉄粉末、ニッケル粉末、銅粉末、鉄合金粉末および黒鉛粉末を用いるとともに、表３に示すように銅粉末の添加量を変えて配合、混合して、原料粉末を得た。次いで、これら原料粉末を、第１実施例と同様に成形、焼結、浸炭焼き入れ、焼き戻しを行って、試料番号１３〜１６の柱状試料（ピン）を作製した。これらの試料につき、第１実施例と同じ相手材を用い、かつ第１実施例と同じ条件でピン・オン・ディスク摩擦摩耗試験を行い、試験後の摩耗量を測定した。このときの試験結果を、表３に併記する。なお、表３には、第１実施例の試料番号０５の値を併せて示している。
[Third embodiment]
While using the iron powder, nickel powder, copper powder, iron alloy powder, and graphite powder of the first example, the addition amount of the copper powder was changed and blended and mixed as shown in Table 3 to obtain a raw material powder. . Subsequently, these raw material powders were molded, sintered, carburized and quenched and tempered in the same manner as in the first example to prepare columnar samples (pins) of sample numbers 13 to 16. These samples were subjected to a pin-on-disk friction and wear test using the same mating material as in the first example and under the same conditions as in the first example, and the amount of wear after the test was measured. The test results at this time are also shown in Table 3. Table 3 also shows the value of sample number 05 of the first example.
表３より、原料粉末への銅粉末添加量（全体組成中のＣｕ量）の影響を調べることができる。すなわち、銅粉末を添加せず、焼結合金基地にＣｕを含有しない試料番号１３の試料は、焼結合金基地の強化および焼き入れ性の改善がなされず、ピン摩耗量が増大している。一方、銅粉末を０．５〜３質量％添加した試料番号１４，０５，１５の試料は、焼結合金基地の強化および焼き入れ性の改善がなされ、ピン摩耗量が半分以上抑制され、合計摩耗量も目標を達成している。 From Table 3, the influence of the amount of copper powder added to the raw material powder (the amount of Cu in the overall composition) can be examined. That is, the sample No. 13 in which the copper powder is not added and the sintered alloy matrix does not contain Cu is not strengthened and hardened, and the pin wear amount is increased. On the other hand, the samples Nos. 14, 05 and 15 to which copper powder is added in an amount of 0.5 to 3% by mass are strengthened in the sintered alloy base and improved in hardenability, and the amount of pin wear is suppressed by more than half. The amount of wear has also reached the target.
しかしながら、銅粉末の添加量が３質量％を超える試料番号１６の試料では、銅粉末の添加量が過多となり、焼結合金基地中に過飽和のＣｕが遊離銅相として析出するようになって焼結合金の強度が低下し、ピン摩耗量が増大している。また、焼結合金基地の焼き入れ性が向上し過ぎて焼結合金基地のマルテンサイトが硬く、かつ脆くなり、ディスクへの攻撃性が増加してディスク摩耗量も増大している。これらのことから、原料粉末への銅粉末添加量（全体組成中のＣｕ量）は０．５〜３質量％とすべきことが確認された。 However, in the sample of Sample No. 16 in which the amount of copper powder added exceeds 3% by mass, the amount of copper powder added is excessive, and supersaturated Cu is precipitated as a free copper phase in the sintered alloy matrix. The strength of the bond gold is reduced and the amount of pin wear is increased. Further, the hardenability of the sintered alloy base is improved too much, the martensite of the sintered alloy base becomes hard and brittle, the aggressiveness to the disk is increased, and the amount of wear of the disk is also increased. From these things, it was confirmed that the amount of copper powder added to the raw material powder (the amount of Cu in the overall composition) should be 0.5 to 3% by mass.
［第４実施例］
上記第１実施例の鉄粉末、ニッケル粉末、銅粉末、および黒鉛粉末を用いるとともに、表４に示す組成の鉄合金粉末を配合、混合して、原料粉末を得た。次いで、これら原料粉末を、第１実施例と同様に成形、焼結、浸炭焼き入れ、焼き戻しを行って、試料番号１７〜２９の柱状試料（ピン）を作製した。これらの試料につき、第１実施例と同じ相手材を用い、かつ第１実施例と同じ条件でピン・オン・ディスク摩擦摩耗試験を行い、試験後の摩耗量を測定した。このときの試験結果を、表４に併記する。なお、表４には、第１実施例の試料番号０５の値を併せて示している。
[Fourth embodiment]
While using the iron powder of the said 1st Example, nickel powder, copper powder, and graphite powder, the iron alloy powder of the composition shown in Table 4 was mix | blended and mixed, and raw material powder was obtained. Subsequently, these raw material powders were molded, sintered, carburized and quenched, and tempered in the same manner as in the first example to prepare columnar samples (pins) of sample numbers 17 to 29. These samples were subjected to a pin-on-disk friction and wear test using the same mating material as in the first example and under the same conditions as in the first example, and the amount of wear after the test was measured. The test results at this time are also shown in Table 4. Table 4 also shows the value of sample number 05 of the first embodiment.
表４の試料番号０５および１７〜２１の試料より、鉄合金粉末中のＣｒ，Ｍｏ，ＷおよびＶの量（硬質相中のＣｒ，Ｍｏ，ＷおよびＶの量）の影響を調べることができる。すなわち、鉄合金粉末中のＣｒ量が１質量％、Ｍｏ量が１質量％、Ｗ量が１質量％およびＶ量が０．５質量％の試料番号１７の試料は、炭化物の析出量が不十分でピン摩耗量が増大している。一方、鉄合金粉末中のＣｒ量が３〜８質量％、Ｍｏ量が３〜８質量％、Ｗ量が３〜８質量％およびＶ量が１〜３質量％の試料番号１８，０５，１９，２０の試料は、十分な炭化物が析出してピン摩耗量が低減している。 From the samples Nos. 05 and 17 to 21 in Table 4, the influence of the amount of Cr, Mo, W and V in the iron alloy powder (the amount of Cr, Mo, W and V in the hard phase) can be examined. . That is, in the sample of Sample No. 17 in which the amount of Cr in the iron alloy powder is 1% by mass, the amount of Mo is 1% by mass, the amount of W is 1% by mass, and the amount of V is 0.5% by mass, the precipitation amount of carbide is not high. Sufficient pin wear is increasing. On the other hand, the sample number 18,05,19 whose Cr amount in iron alloy powder is 3-8 mass%, Mo amount is 3-8 mass%, W amount is 3-8 mass%, and V amount is 1-3 mass%. , 20 has a sufficient amount of carbides deposited to reduce pin wear.
しかしながら、鉄合金粉末中のＣｒ量が１０質量％、Ｍｏ量が１０質量％、Ｗ量が１０質量％およびＶ量が５質量％の試料番号２１の試料では、鉄合金粉末中の合金元素が過多となって鉄合金粉末が硬くなり、原料粉末の圧縮性が低下し、成形体密度の低下を招く結果、焼結体密度が低下して焼結体の強度が低下することにより、ピン摩耗量が増大している。また、ピンの摩耗粉が研磨粒子として作用することにより、ディスク摩耗量も増大している。これらのことから、鉄合金粉末中のＣｒ量（硬質相中のＣｒ量）は３〜８質量％、鉄合金粉末中のＭｏ量（硬質相中のＭｏ量）は３〜８質量％、鉄合金粉末中のＷ量（硬質相中のＷ量）は３〜８質量％、および鉄合金粉末中のＶ量（硬質相中のＶ量）は１〜３質量％とすべきことが確認された。 However, in the sample No. 21 in which the amount of Cr in the iron alloy powder is 10% by mass, the amount of Mo is 10% by mass, the amount of W is 10% by mass, and the amount of V is 5% by mass, the alloy elements in the iron alloy powder are As a result of excess, the iron alloy powder becomes hard, the compressibility of the raw material powder decreases, and the density of the compact is reduced. As a result, the density of the sintered body decreases and the strength of the sintered body decreases. The amount is increasing. Further, the amount of wear of the disk is increased due to the abrasion powder of the pins acting as abrasive particles. From these, the amount of Cr in the iron alloy powder (the amount of Cr in the hard phase) is 3 to 8% by mass, the amount of Mo in the iron alloy powder (the amount of Mo in the hard phase) is 3 to 8% by mass, iron It was confirmed that the W amount in the alloy powder (W amount in the hard phase) should be 3-8% by mass, and the V amount in the iron alloy powder (V amount in the hard phase) should be 1-3% by mass. It was.
また、表４の試料番号０５および２２〜２５の試料より、鉄合金粉末中のＳｉ量（硬質相中のＳｉ量）の影響を調べることができる。すなわち、鉄合金粉末中のＳｉ量が０．１質量％に満たない試料番号２２の試料は、鉄合金粉末の脱酸が不十分であり、強固な酸化被膜によって焼結が進行し難く、そのためピン摩耗量が増大している。一方、鉄合金粉末中のＳｉ量が０．１〜１質量％の試料番号２３、０５、２４の試料は、鉄合金粉末の脱酸が十分で焼結が進行し易く、かつ硬質相のＦｅ基地の強化作用および金属炭化物の生成作用により摩耗量が低減している。 Moreover, the influence of the Si amount in the iron alloy powder (the Si amount in the hard phase) can be examined from the samples Nos. 05 and 22 to 25 in Table 4. That is, in the sample of sample number 22 in which the amount of Si in the iron alloy powder is less than 0.1% by mass, deoxidation of the iron alloy powder is insufficient, and sintering is difficult to proceed due to a strong oxide film. Pin wear has increased. On the other hand, the samples Nos. 23, 05, and 24 having the Si amount in the iron alloy powder of 0.1 to 1% by mass were sufficiently deoxidized and easily progressed in sintering, and the hard phase Fe The amount of wear is reduced by the strengthening action of the base and the production action of metal carbide.
しかしながら、鉄合金粉末中のＳｉ量が１質量％を超える試料番号２５の試料では、鉄合金粉末中のＳｉが過多となって鉄合金粉末が硬くなり、原料粉末の圧縮性が低下し、成形体密度の低下を招く結果、焼結体密度が低下して焼結体の強度が低下することにより、ピン摩耗量が増大している。また、ピンの摩耗粉が研磨粒子として作用することにより、ディスク摩耗量も増大している。これらのことから、鉄合金粉末中のＳｉ量（硬質相中のＳｉ量）は０．１〜１質量％とすべきことが確認された。 However, in the sample of sample number 25 in which the amount of Si in the iron alloy powder exceeds 1% by mass, the amount of Si in the iron alloy powder becomes excessive, the iron alloy powder becomes hard, the compressibility of the raw material powder decreases, and molding is performed. As a result of the decrease in the body density, the sintered body density is decreased and the strength of the sintered body is decreased, so that the pin wear amount is increased. Further, the amount of wear of the disk is increased due to the abrasion powder of the pins acting as abrasive particles. From these facts, it was confirmed that the amount of Si in the iron alloy powder (the amount of Si in the hard phase) should be 0.1 to 1% by mass.
また、表４の試料番号０５および２６〜２９の試料より、鉄合金粉末中のＣ量の影響を調べることができる。すなわち、鉄合金粉末中のＣ量が０．８質量％に満たない試料番号２６の試料は、鉄合金粉末中に固溶する合金元素が過多となって鉄合金粉末が硬くなり、原料粉末の圧縮性を損なう結果、成形体密度の低下に伴い焼結体密度が低下し、焼結体の強度が低下するためピン摩耗量が増大するとともに、ピンの摩耗粉が研磨粒子として作用してディスク摩耗量も増大している。一方、鉄合金粉末中のＣ量が０．８〜１．４質量％の試料番号２７、０５、２８の試料は、鉄合金粉末中のＣと合金元素が結合して鉄合金粉末中に既に金属炭化物として析出し、鉄合金粉末中に固溶する合金元素量が低下する結果、鉄合金粉末の硬さが低下して原料粉末の圧縮性が改善され、摩耗量が低減している。 Moreover, the influence of the amount of C in iron alloy powder can be investigated from the sample numbers 05 and 26-29 of Table 4. That is, in the sample No. 26 in which the amount of C in the iron alloy powder is less than 0.8% by mass, the alloy element dissolved in the iron alloy powder becomes excessive, and the iron alloy powder becomes harder. As a result of the loss of compressibility, the density of the sintered body decreases with a decrease in the density of the molded body, and the strength of the sintered body decreases, so that the amount of pin wear increases and the pin wear powder acts as abrasive particles. The amount of wear is also increasing. On the other hand, samples Nos. 27, 05, and 28 in which the amount of C in the iron alloy powder is 0.8 to 1.4% by mass are already in the iron alloy powder due to the combination of C in the iron alloy powder and the alloy element. As a result of a decrease in the amount of alloying elements precipitated as metal carbide and dissolved in the iron alloy powder, the hardness of the iron alloy powder is reduced, the compressibility of the raw material powder is improved, and the amount of wear is reduced.
しかしながら、鉄合金粉末中のＣ量が１．４質量％を超える試料番号２９の試料では、鉄合金粉末中に析出する金属炭化物の量が過多となって鉄合金粉末が硬くなり、原料粉末の圧縮性を損なう結果、ピン摩耗量およびディスク摩耗量ともに増大する。これらのことから、鉄合金粉末中のＣ量は、０．１〜１．４質量％とすべきことが確認された。 However, in the sample of Sample No. 29 in which the amount of C in the iron alloy powder exceeds 1.4% by mass, the amount of metal carbide precipitated in the iron alloy powder becomes excessive, and the iron alloy powder becomes hard, As a result of impairing compressibility, both pin wear and disk wear increase. From these facts, it was confirmed that the amount of C in the iron alloy powder should be 0.1 to 1.4% by mass.
［第５実施例］
上記第１実施例の鉄粉末、ニッケル粉末、銅粉末、鉄合金粉末および黒鉛粉末を用いるとともに、表５に示すように黒鉛粉末の添加量を変えて配合、混合して、原料粉末を得た。次いで、これら原料粉末を、第１実施例と同様に成形、焼結、浸炭焼き入れ、焼き戻しを行って、試料番号３０〜３４の柱状試料（ピン）を作製した。これらの試料につき、第１実施例と同じ相手材を用い、かつ第１実施例と同じ条件でピン・オン・ディスク摩擦摩耗試験を行い、試験後の摩耗量を測定した。このときの試験結果を、表５に併記する。なお、表５には、第１実施例の試料番号０５の値を併せて示している。また、この第５実施例では、上記の試料番号３０〜３４の試料および第１実施例の試料番号０５につき、炭素分析を併せて行って結合炭素量を測定した。その結果を表５に併せて示す。
[Fifth embodiment]
While using the iron powder, nickel powder, copper powder, iron alloy powder, and graphite powder of the first example, the raw material powder was obtained by mixing and mixing with the addition amount of the graphite powder as shown in Table 5 . Subsequently, these raw material powders were molded, sintered, carburized and quenched and tempered in the same manner as in the first example to prepare columnar samples (pins) of sample numbers 30 to 34. These samples were subjected to a pin-on-disk friction and wear test using the same mating material as in the first example and under the same conditions as in the first example, and the amount of wear after the test was measured. The test results at this time are also shown in Table 5. Table 5 also shows the value of sample number 05 of the first example. Moreover, in this 5th Example, carbon analysis was performed collectively about the sample of the said sample numbers 30-34, and the sample number 05 of 1st Example, and the amount of bond carbon was measured. The results are also shown in Table 5.
表５より、原料粉末への黒鉛粉末添加量および全体組成中のＣ量の影響を調べることができる。すなわち、原料粉末への黒鉛粉末添加量が０．３質量％に満たない試料番号３０の試料は、焼結体のＣ量が乏しい結果、浸炭焼き入れによっても十分なＣ量が得られず、基地が低炭素のマルテンサイトとなって強度が不十分となりピン摩耗量が増加している。一方、原料粉末への黒鉛粉末添加量が０．３質量％の試料番号３１の試料は、浸炭焼き入れ後十分なＣ量が得られ、ピン摩耗量が低減している。このときの結合Ｃ量（全体組成中のＣ量）は０．７質量％である。そして、原料粉末への黒鉛粉末添加量が０．５〜１質量％の試料番号３２、０５、３３の試料は、結合Ｃ量（全体組成中のＣ量）が０．８〜１質量％となり、さらにピン摩耗量が低減している。 From Table 5, the influence of the amount of graphite powder added to the raw material powder and the amount of C in the overall composition can be examined. That is, the sample of sample number 30 in which the amount of graphite powder added to the raw material powder is less than 0.3% by mass, the C amount of the sintered body is poor, so a sufficient amount of C cannot be obtained even by carburizing and quenching. The base becomes low-carbon martensite and the strength is insufficient and the amount of pin wear increases. On the other hand, the sample No. 31 in which the amount of graphite powder added to the raw material powder is 0.3% by mass has a sufficient amount of C after carburizing and quenching, and the amount of pin wear is reduced. The amount of bonded C (the amount of C in the entire composition) at this time is 0.7% by mass. And the sample numbers 32, 05, and 33 in which the amount of graphite powder added to the raw material powder is 0.5 to 1% by mass, the bonded C amount (C amount in the entire composition) is 0.8 to 1% by mass. Further, the amount of pin wear is reduced.
しかしながら、原料粉末への黒鉛粉末添加量が１質量％を超える試料番号３４の試料では、結合Ｃ量（全体組成中のＣ量）が１質量％を超えているため、基地が硬く、かつ脆くなるとともに、相手材への攻撃性が増加して、ピン摩耗量およびディスク摩耗量ともに増加している。これらのことから、原料粉末への黒鉛粉末添加量は０．３〜１質量％とすべきであり、かつ全体組成中のＣ量は０．７〜１質量％とすべきことが確認された。 However, in the sample of Sample No. 34 in which the amount of graphite powder added to the raw material powder exceeds 1% by mass, the bond C amount (C amount in the entire composition) exceeds 1% by mass, so the base is hard and brittle. At the same time, the aggressiveness against the mating material has increased, and both the pin wear amount and the disk wear amount have increased. From these facts, it was confirmed that the amount of graphite powder added to the raw material powder should be 0.3 to 1% by mass, and the amount of C in the overall composition should be 0.7 to 1% by mass. .
１…ガバナシャフト
２…ガバナウエイトホルダ
３…ピン
４…ガバナウエイト
４ａ…ガバナウエイトの爪部
５…ガバナスリーブ
５ａ…ガバナスリーブの鍔部
６…シフタ
７…ガバナレバー
８…レバー軸
９…スプリング
１０…ガバナリンク
１１…コントロールラック
1 ...
Claims (4)
全体組成が、質量比で、Ｎｉ：１〜５％、Ｃｕ：０．５〜３％、Ｃｒ：０．６〜４％、Ｍｏ：０．６〜４％、Ｖ：０．２〜１．５％、Ｗ：０．６〜４％、Ｓｉ：０．０２〜０．５％、Ｃ：０．７〜１％、および残部がＦｅと不可避不純物からなるとともに、
Ｎｉリッチのオーステナイト相が分散するマルテンサイト基地中に、Ｆｅ基合金基地中にＣｒ，Ｍｏ，Ｗ，Ｖの炭化物が群状に析出分散する硬質相が２０〜５０質量％分散する金属組織を呈する焼結合金からなること
を特徴とするガバナウエイト。 A governor weight used in a governor device of a fuel injection pump,
The overall composition is, by mass ratio, Ni: 1 to 5%, Cu: 0.5 to 3%, Cr: 0.6 to 4%, Mo: 0.6 to 4%, V: 0.2 to 1. 5%, W: 0.6-4%, Si: 0.02-0.5%, C: 0.7-1%, and the balance consists of Fe and inevitable impurities,
In the martensite matrix in which the Ni-rich austenite phase is dispersed, a hard phase in which carbides of Cr, Mo, W, and V are precipitated and dispersed in a group form in the Fe-based alloy matrix has a metal structure dispersed in an amount of 20 to 50% by mass. A governor weight comprising a sintered alloy.
組成が、質量比で、Ｃｒ：３〜８％、Ｍｏ：３〜８％、Ｖ：１〜３％、Ｗ：３〜８％、Ｓｉ：０．１〜１％、Ｃ：０．８〜１．４％、および残部がＦｅと不可避不純物からなる鉄合金粉末を２０〜５０質量％と、
ニッケル粉末を１〜５質量％と、
銅粉末を０．５〜３質量％と、
黒鉛粉末を０．３〜１質量％と
を添加し、混合して原料粉末を得、
該原料粉末を、所望の形状に圧粉成形し、次いで、得られた成形体を焼結し、次いで、得られた焼結体を浸炭焼き入れした後、焼き戻しを行うこと
を特徴とする燃料噴射ポンプのガバナ装置に用いられるガバナウエイトの製造方法。 Iron powder,
Composition is mass ratio, Cr: 3-8%, Mo: 3-8%, V: 1-3%, W: 3-8%, Si: 0.1-1%, C: 0.8- 1.4-50%, and the iron alloy powder consisting of Fe and inevitable impurities in the balance, 20-50% by mass,
1 to 5% by mass of nickel powder,
0.5-3 mass% copper powder,
Add 0.3-1 mass% of graphite powder and mix to obtain raw material powder,
The raw material powder is compacted into a desired shape, then the obtained molded body is sintered, and then the obtained sintered body is carburized and quenched, and then tempered. A governor weight manufacturing method used in a governor device of a fuel injection pump.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008174734A JP5171440B2 (en) | 2008-07-03 | 2008-07-03 | Governor weight and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008174734A JP5171440B2 (en) | 2008-07-03 | 2008-07-03 | Governor weight and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2010014023A true JP2010014023A (en) | 2010-01-21 |
| JP5171440B2 JP5171440B2 (en) | 2013-03-27 |
Family
ID=41700343
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2008174734A Expired - Fee Related JP5171440B2 (en) | 2008-07-03 | 2008-07-03 | Governor weight and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP5171440B2 (en) |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH1046298A (en) * | 1996-08-05 | 1998-02-17 | Hitachi Powdered Metals Co Ltd | Wear resistant sintered alloy for valve seat of internal combustion engine excellent in corrosion resistance and its production |
| JP2000064003A (en) * | 1998-08-19 | 2000-02-29 | Hitachi Powdered Metals Co Ltd | Wear resistant sintered alloy and its production |
| JP2003161169A (en) * | 2001-11-29 | 2003-06-06 | Yanmar Co Ltd | Sliding members for fuel injection pumps |
| JP2003253406A (en) * | 2002-03-01 | 2003-09-10 | Jfe Steel Kk | Highly wear-resistant and high strength sintered parts, and production method thereof |
| JP2005154796A (en) * | 2003-11-21 | 2005-06-16 | Hitachi Powdered Metals Co Ltd | Wear-resistant sintered alloy and its production method |
| JP2008063663A (en) * | 2007-09-14 | 2008-03-21 | Komatsu Ltd | Copper sintered sliding material and sintered sliding member using the same |
-
2008
- 2008-07-03 JP JP2008174734A patent/JP5171440B2/en not_active Expired - Fee Related
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH1046298A (en) * | 1996-08-05 | 1998-02-17 | Hitachi Powdered Metals Co Ltd | Wear resistant sintered alloy for valve seat of internal combustion engine excellent in corrosion resistance and its production |
| JP2000064003A (en) * | 1998-08-19 | 2000-02-29 | Hitachi Powdered Metals Co Ltd | Wear resistant sintered alloy and its production |
| JP2003161169A (en) * | 2001-11-29 | 2003-06-06 | Yanmar Co Ltd | Sliding members for fuel injection pumps |
| JP2003253406A (en) * | 2002-03-01 | 2003-09-10 | Jfe Steel Kk | Highly wear-resistant and high strength sintered parts, and production method thereof |
| JP2005154796A (en) * | 2003-11-21 | 2005-06-16 | Hitachi Powdered Metals Co Ltd | Wear-resistant sintered alloy and its production method |
| JP2008063663A (en) * | 2007-09-14 | 2008-03-21 | Komatsu Ltd | Copper sintered sliding material and sintered sliding member using the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JP5171440B2 (en) | 2013-03-27 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP4183346B2 (en) | Mixed powder for powder metallurgy, iron-based sintered body and method for producing the same | |
| JP2648519B2 (en) | Method of manufacturing synchronizer hub | |
| JP4368245B2 (en) | Hard particle dispersion type iron-based sintered alloy | |
| JP5992402B2 (en) | Manufacturing method of nitrided sintered component | |
| TW201107495A (en) | High strength low alloyed sintered steel | |
| CN103031499A (en) | Iron-based sintered sliding member and production method therefor | |
| EP2778243B1 (en) | Iron based sintered sliding member and method for producing the same | |
| KR101607744B1 (en) | Iron base sintered alloy for sliding member and method for manufacturing the same | |
| CN103361576A (en) | Sintered alloy for valve seat and manufacturing method of exhaust valve seat using the same | |
| JP5100487B2 (en) | Manufacturing method of sintered machine parts | |
| CN105980590B (en) | Steel alloy and the component for including such steel alloy | |
| JP6229281B2 (en) | Iron-based sintered alloy and method for producing the same | |
| JP2004307950A (en) | Iron-based sintered alloy, valve seat ring, raw material powder for producing iron-based sintered alloy and method of producing iron-based sintered alloy | |
| JP6515955B2 (en) | Method of manufacturing mixed powder for powder metallurgy and iron-based sintered body | |
| US20180080104A1 (en) | Manufacturing method of wear-resistant iron-based sintered alloy and wear-resistant iron-based sintered alloy | |
| JP5171440B2 (en) | Governor weight and manufacturing method thereof | |
| JP6528899B2 (en) | Method of manufacturing mixed powder and sintered body for powder metallurgy | |
| JP4069506B2 (en) | Alloy steel powder and mixed powder for high strength sintered parts | |
| JPH05202451A (en) | Sintered alloy for valve seat | |
| JP2005330573A (en) | Alloy steel powder for powder metallurgy | |
| JP4702803B2 (en) | Manufacturing method of sintered machine parts | |
| JP4005189B2 (en) | High strength sintered steel and method for producing the same | |
| JPH0959740A (en) | Powder mixture for powder metallurgy and its sintered compact | |
| JP5253132B2 (en) | Wear-resistant sintered alloy and method for producing the same | |
| JP6627856B2 (en) | Method for producing powder mixture for powder metallurgy and sintered body |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20110527 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20120928 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20120928 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20121114 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20121203 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20121225 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 5171440 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| R360 | Written notification for declining of transfer of rights |
Free format text: JAPANESE INTERMEDIATE CODE: R360 |
|
| R360 | Written notification for declining of transfer of rights |
Free format text: JAPANESE INTERMEDIATE CODE: R360 |
|
| R371 | Transfer withdrawn |
Free format text: JAPANESE INTERMEDIATE CODE: R371 |
|
| LAPS | Cancellation because of no payment of annual fees |