JP2011105979A - Mo-Co BASED ALLOY - Google Patents
Mo-Co BASED ALLOY Download PDFInfo
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- JP2011105979A JP2011105979A JP2009260468A JP2009260468A JP2011105979A JP 2011105979 A JP2011105979 A JP 2011105979A JP 2009260468 A JP2009260468 A JP 2009260468A JP 2009260468 A JP2009260468 A JP 2009260468A JP 2011105979 A JP2011105979 A JP 2011105979A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 54
- 239000000956 alloy Substances 0.000 title claims abstract description 54
- 229910017313 Mo—Co Inorganic materials 0.000 title claims abstract description 17
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 description 24
- 229910052751 metal Inorganic materials 0.000 description 13
- 239000002184 metal Substances 0.000 description 13
- 238000012360 testing method Methods 0.000 description 11
- 230000013011 mating Effects 0.000 description 8
- 238000000034 method Methods 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 238000000151 deposition Methods 0.000 description 5
- 230000002093 peripheral effect Effects 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 239000000853 adhesive Substances 0.000 description 4
- 230000001070 adhesive effect Effects 0.000 description 4
- 239000012298 atmosphere Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000002485 combustion reaction Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 238000007429 general method Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000004372 laser cladding Methods 0.000 description 2
- 239000011812 mixed powder Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- -1 and is in mass% Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000005382 thermal cycling Methods 0.000 description 1
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- Powder Metallurgy (AREA)
Abstract
Description
本発明は、Ｍｏ−Ｃｏ基合金に関し、特に、部材に盛金されるＭｏ−Ｃｏ基合金に関する。 The present invention relates to a Mo—Co based alloy, and particularly to a Mo—Co based alloy deposited on a member.
部材は、使用環境に応じた材料で構成される。高温環境で使用される部材は、耐熱性に優れた材料で構成される。また、相手部材に繰り返し接触する部材は、耐摩耗性に優れた材料で構成される。 A member is comprised with the material according to use environment. A member used in a high temperature environment is made of a material having excellent heat resistance. Further, the member that repeatedly contacts the mating member is made of a material having excellent wear resistance.
例えば、車両用のエンジンバルブのバルブフェースは、エンジン作動時に、燃焼雰囲気に曝され、金属製のバルブシートに繰り返し接触するので、耐熱性、耐摩耗性に優れた材料（例えば、ＳＵＨ３５等のオーステナイト鋼）で構成される。 For example, a valve face of an engine valve for a vehicle is exposed to a combustion atmosphere during engine operation and repeatedly contacts a metal valve seat, so that a material having excellent heat resistance and wear resistance (for example, austenite such as SUH35). Steel).
しかし、部材に要求される全ての特性を単一の材料で満たすことは難しい。また、相手部材に繰り返し接触するのは、部材の表面全体ではなく、部材の表面の一部である。こうした事情から、部材の表面の一部に、耐摩耗性に優れた合金からなる盛金部が設けられている。 However, it is difficult to satisfy all the properties required for a member with a single material. Moreover, it is not a whole surface of a member but a part of the surface of a member that contacts a partner member repeatedly. For these reasons, a banking portion made of an alloy having excellent wear resistance is provided on a part of the surface of the member.
盛金部に用いられる合金としては、例えばＭｏ−Ｃｏ基合金等がある（例えば、特許文献１参照）。この合金には、Ｃが添加されている。Ｃは、金属炭化物を形成し、合金の硬さを向上させ、耐摩耗性を向上させる。この合金は、部材であるバルブフェースの表面に盛金されると、エンジン作動時に、燃焼雰囲気中の酸素と反応し酸化被膜で覆われる。これにより、部材と相手部材との金属接触を抑制することができ、凝着摩耗を低減させることができる。 Examples of the alloy used for the metal bank include a Mo—Co based alloy (see, for example, Patent Document 1). C is added to this alloy. C forms a metal carbide, improves the hardness of the alloy, and improves the wear resistance. When this alloy is deposited on the surface of the valve face as a member, it reacts with oxygen in the combustion atmosphere and is covered with an oxide film during engine operation. Thereby, the metal contact of a member and the other party member can be controlled, and adhesive wear can be reduced.
しかし、従来のＭｏ−Ｃｏ基合金では、使用温度が高くなると、酸化被膜が多量に形成され、酸化被膜が剥離しやすくなる。酸化被膜が相手部材との接触によって部分的に剥離すると、合金表面が荒れ、相手部材を摩耗させる相手攻撃性が増大する。 However, in the conventional Mo—Co base alloy, when the use temperature is increased, a large amount of oxide film is formed, and the oxide film is easily peeled off. When the oxide film is partially peeled by contact with the mating member, the alloy surface is roughened, and the mating aggressiveness that wears the mating member increases.
本発明は、上記に鑑みてなされたものであって、耐摩耗性に優れ、且つ、表面の酸化被膜が剥離し難いＭｏ−Ｃｏ基合金を提供することを目的とする。 This invention is made | formed in view of the above, Comprising: It aims at providing the Mo-Co base alloy which is excellent in abrasion resistance, and the surface oxide film cannot peel easily.
前記目的を達成するため、本発明のＭｏ−Ｃｏ基合金は、
質量％で、Ｍｏ：２０〜７０％、Ｃ：０．５〜３．０％、Ｙ：０．１〜１．５％、残部Ｃｏおよび不可避的不純物からなる。
In order to achieve the above object, the Mo—Co based alloy of the present invention is:
It consists of Mo: 20 to 70%, C: 0.5 to 3.0%, Y: 0.1 to 1.5%, the balance Co and inevitable impurities.
本発明によれば、耐摩耗性に優れ、且つ、表面の酸化被膜が剥離し難いＭｏ−Ｃｏ基合金を提供することができる。 According to the present invention, it is possible to provide a Mo—Co based alloy that is excellent in wear resistance and in which an oxide film on the surface is hardly peeled off.
以下、図面を参照し、本発明を実施するための形態について説明する。 Hereinafter, embodiments for carrying out the present invention will be described with reference to the drawings.
部材（以下、「母材」ともいう）は、使用環境に応じた材料で構成される。高温環境で使用される部材は、耐熱性に優れた材料で構成される。また、相手部材に繰り返し接触する部材は、耐摩耗性に優れた材料で構成される。 The member (hereinafter also referred to as “base material”) is made of a material corresponding to the use environment. A member used in a high temperature environment is made of a material having excellent heat resistance. Further, the member that repeatedly contacts the mating member is made of a material having excellent wear resistance.
例えば、図１に示すように、車両用のエンジンバルブ（排気バルブや吸気バルブ）１０のバルブフェース１１は、エンジン作動時に、燃焼雰囲気に曝され、金属製のバルブシート１２に繰り返し接触するので、耐熱性、耐摩耗性に優れた材料（例えば、ＳＵＨ３５等のオーステナイト鋼）で構成される。 For example, as shown in FIG. 1, a valve face 11 of an engine valve (exhaust valve or intake valve) 10 for a vehicle is exposed to a combustion atmosphere during engine operation, and repeatedly contacts a metal valve seat 12. It is made of a material excellent in heat resistance and wear resistance (for example, austenitic steel such as SUH35).
しかし、母材１１に要求される全ての特性を単一の材料で満たすことは難しい。また、相手部材１２に繰り返し接触するのは、母材１１の表面全体ではなく、母材１１の外周面である。こうした事情から、母材１１の外周面に、耐摩耗性に優れた合金からなる盛金部１３が設けられている。 However, it is difficult to satisfy all the characteristics required for the base material 11 with a single material. Further, it is not the entire surface of the base material 11 that repeatedly contacts the mating member 12 but the outer peripheral surface of the base material 11. For these reasons, a metal plate 13 made of an alloy having excellent wear resistance is provided on the outer peripheral surface of the base material 11.
尚、図１に示す例では、母材の形状は、略円板状であるが、本発明はこれに限定されず、例えば、棒状であっても良いし、環状であっても良い。また、図１に示す例では、合金を盛金する箇所は、母材の外周面であるが、本発明はこれに限定されない。要は、相手部材に繰り返し接触する部分に合金が盛金されていれば良い。 In the example shown in FIG. 1, the shape of the base material is a substantially disk shape, but the present invention is not limited to this, and may be, for example, a rod shape or an annular shape. Moreover, in the example shown in FIG. 1, the place where the alloy is plated is the outer peripheral surface of the base material, but the present invention is not limited to this. In short, it is only necessary that the alloy is deposited on the portion that repeatedly contacts the mating member.
盛金部を設ける方法は、一般的な方法であって良く、例えば、プラズマアーク法やレーザクラッド法が用いられる。プラズマアーク法やレーザクラッド法を用いる場合、盛金部用の合金は、粉末の形態で使用されて良い。合金の塊を粉末にする方法は、一般的な方法であって良く、例えば、アトマイズ法が用いられる。 The method for providing the raised portion may be a general method, and for example, a plasma arc method or a laser cladding method is used. When the plasma arc method or the laser cladding method is used, the alloy for the depositing part may be used in the form of powder. The method of turning the alloy lump into powder may be a general method, for example, an atomizing method is used.
盛金部に用いられる合金は、Ｍｏ−Ｃｏ基合金であって、質量％で、Ｍｏ：２０〜７０％、Ｃ：０．５〜３．０％、Ｙ：０．１〜１．５％、残部Ｃｏおよび不可避的不純物からなる。このＭｏ−Ｃｏ基合金は、質量％で、Ｃｒ：１５％以下、Ｎｉ：４０％以下含有して良い。 The alloy used for the depositing part is a Mo-Co based alloy, and is in mass%, Mo: 20 to 70%, C: 0.5 to 3.0%, Y: 0.1 to 1.5%. And the balance Co and inevitable impurities. This Mo—Co based alloy may be contained in mass%, Cr: 15% or less, Ni: 40% or less.
次に、上記Ｍｏ−Ｃｏ基合金の各成分について説明する。 Next, each component of the Mo—Co based alloy will be described.
Ｍｏは、必須成分であって、Ｍｏ炭化物を形成し、合金の耐摩耗性を向上させる。また、Ｍｏは、合金表面に酸化被膜を形成する。これにより、部材と相手部材との金属接触を抑制することができ、凝着摩耗を抑制することができる。但し、Ｍｏ含有量が２０質量％未満であると、上記効果が十分に得られない。一方、Ｍｏ含有量が７０質量％を超えると、Ｍｏ炭化物が多量に形成され、合金の硬さが高くなり過ぎ、相手部材を摩耗させる相手攻撃性が高くなる。また、Ｍｏ含有量が多過ぎると、母材がオーステナイト鋼の場合、母材と合金との線膨張係数差が大きくなり過ぎるので、熱サイクルによって合金割れが発生し易くなる。よって、Ｍｏ含有量は、２０〜７０質量％とした。より好ましい範囲は、２０〜５０質量％である。 Mo is an essential component, forms Mo carbide, and improves the wear resistance of the alloy. Mo forms an oxide film on the alloy surface. Thereby, the metal contact between the member and the mating member can be suppressed, and adhesion wear can be suppressed. However, the said effect is not fully acquired as Mo content is less than 20 mass%. On the other hand, when the Mo content exceeds 70% by mass, a large amount of Mo carbide is formed, the hardness of the alloy becomes too high, and the opponent attacking property of wearing the counterpart member becomes high. On the other hand, if the Mo content is too large, when the base material is austenitic steel, the difference in linear expansion coefficient between the base material and the alloy becomes too large, and alloy cracking is likely to occur due to the heat cycle. Therefore, the Mo content is set to 20 to 70% by mass. A more preferable range is 20 to 50% by mass.
Ｃは、必須成分であって、金属炭化物を形成すると共に、固溶ならびに遊離黒鉛の形成により、合金の硬さを向上させ、耐摩耗性を向上させる。但し、Ｃ含有量が０．５質量％未満では、上記効果が十分に得られず、３質量％を超えると合金の硬さが高くなり過ぎ、相手部材を摩耗させる相手攻撃性が高くなる。よって、Ｃ含有量は、０．５〜３．０質量％とした。より好ましい範囲は、０．５〜１．５質量％である。 C is an essential component, and forms metal carbide, and improves the hardness of the alloy and improves wear resistance by forming solid solution and free graphite. However, if the C content is less than 0.5% by mass, the above effect cannot be obtained sufficiently. If the C content exceeds 3% by mass, the hardness of the alloy becomes too high, and the opponent attacking ability to wear the counterpart member becomes high. Therefore, the C content is set to 0.5 to 3.0% by mass. A more preferable range is 0.5 to 1.5% by mass.
Ｙは、必須成分であって、合金表面に緻密な酸化被膜を形成して、合金内部の酸化を抑制すると共に、酸化被膜が剥離するのを抑制する。但し、Ｙ含有量が０．１質量％未満では、上記効果が十分に得られず、１．５質量％を超えると、合金の硬さが高くなり過ぎ、相手攻撃性が高くなる。また、Ｙ含有量が多過ぎると、合金の耐衝撃性や靱性が低くなるし、コストが高くなる。よって、Ｙ含有量は、０．１〜１．５質量％とした。 Y is an essential component, and forms a dense oxide film on the surface of the alloy to suppress oxidation inside the alloy and to suppress peeling of the oxide film. However, if the Y content is less than 0.1% by mass, the above effects cannot be obtained sufficiently. If the Y content exceeds 1.5% by mass, the hardness of the alloy becomes too high, and the opponent attack becomes high. Moreover, when there is too much Y content, the impact resistance and toughness of an alloy will become low, and cost will become high. Therefore, the Y content is set to 0.1 to 1.5% by mass.
Ｃｒは、必須成分ではなく、任意成分であるが、凝着摩耗を抑制するのに十分な酸化被膜ができる温度を制御する効果がある。Ｃｒ含有量が多くなるほど、酸化被膜ができる温度が高くなる。また、母材がオーステナイト鋼の場合には、Ｃｒ添加によって、合金と母材との線膨張係数差を小さくすることができ、熱サイクルによって合金割れが発生するのを抑制できる。但し、Ｃｒ含有量が１５質量％を超えると、酸化被膜ができる温度が高くなり過ぎるので、凝着摩耗を十分に抑制することができない。よって、Ｃｒ含有量は、１５質量％以下とする。 Cr is not an essential component but an optional component, but has the effect of controlling the temperature at which a sufficient oxide film can be formed to suppress adhesive wear. The higher the Cr content, the higher the temperature at which the oxide film can be formed. When the base material is austenitic steel, the addition of Cr can reduce the difference in linear expansion coefficient between the alloy and the base material, and can suppress the occurrence of alloy cracking due to the thermal cycle. However, if the Cr content exceeds 15% by mass, the temperature at which an oxide film can be formed becomes too high, so that adhesive wear cannot be sufficiently suppressed. Therefore, Cr content shall be 15 mass% or less.
Ｎｉは、必須成分ではなく、任意成分であるが、合金の耐衝撃性を向上させる。Ｎｉ含有量が４０％を超えると、金属炭化物の形成が抑制され、合金の硬さが低くなり過ぎるので、耐摩耗性が低下する。よって、Ｎｉ含有量は、４０質量％以下とする。 Ni is not an essential component but an optional component, but improves the impact resistance of the alloy. If the Ni content exceeds 40%, the formation of metal carbide is suppressed, and the hardness of the alloy becomes too low, so that the wear resistance decreases. Therefore, the Ni content is 40% by mass or less.
尚、Ｆｅは、不可避的不純物として含まれる場合を除き、積極的には含まれない。Ｆｅが含まれると、合金の硬さが低減し、耐摩耗性が低下する。 Note that Fe is not actively included unless it is included as an inevitable impurity. When Fe is contained, the hardness of the alloy is reduced and the wear resistance is reduced.
次に、車両用のエンジンバルブの詳細について再び図１を参照して説明する。 Next, details of the engine valve for the vehicle will be described with reference to FIG. 1 again.
車両用のエンジンバルブ１０は、軸方向（図１では矢印Ａ方向）に往復動するように構成され、カム１４によって往動方向に駆動され、スプリング１５によって復動方向に付勢される。エンジンバルブ１０の先端には略円板状のバルブフェース１１が固定されており、バルブフェース１１の外周面には盛金部１３が溶着されている。バルブフェース１１及び盛金部１３は、エンジンバルブ１０の往復動に連動して、環状のバルブシート１２の開口を開閉する。この際に、盛金部１３がバルブシート１２に繰り返し接触する。 The vehicle engine valve 10 is configured to reciprocate in the axial direction (in the direction of arrow A in FIG. 1), is driven in the forward movement direction by the cam 14, and is urged in the backward movement direction by the spring 15. A substantially disc-like valve face 11 is fixed to the tip of the engine valve 10, and a depositing portion 13 is welded to the outer peripheral surface of the valve face 11. The valve face 11 and the depositing portion 13 open and close the opening of the annular valve seat 12 in conjunction with the reciprocating motion of the engine valve 10. At this time, the metal bank 13 repeatedly contacts the valve seat 12.
盛金部１３の材料には、上記組成のＭｏ−Ｃｏ基合金が用いられる。この合金には、Ｃが添加されているので、合金の耐摩耗性を向上させることができる。また、この合金には、Ｙが添加されているので、緻密な酸化被膜を合金表面に形成することができ、酸化被膜の剥離を抑制することができる。よって、バルブフェース１１とバルブシート１２との金属接触を効果的に抑制することができ、凝着摩耗を効果的に抑制することができる。 As the material for the metal bank 13, a Mo—Co based alloy having the above composition is used. Since C is added to this alloy, the wear resistance of the alloy can be improved. Further, since Y is added to this alloy, a dense oxide film can be formed on the surface of the alloy, and peeling of the oxide film can be suppressed. Therefore, metal contact between the valve face 11 and the valve seat 12 can be effectively suppressed, and adhesive wear can be effectively suppressed.
以上、本発明の実施形態について詳説したが、本発明は、上述した実施形態に制限されることはなく、本発明の範囲を逸脱することなく、上述した実施形態に種々の変形及び置換を加えることができる。 Although the embodiments of the present invention have been described in detail above, the present invention is not limited to the above-described embodiments, and various modifications and substitutions are made to the above-described embodiments without departing from the scope of the present invention. be able to.
例えば、上述した実施形態のＭｏ−Ｃｏ基合金は、盛金部に用いられるとしたが、本発明はこれに限定されない。例えば、部材（母材）に用いられても良い。 For example, although the Mo—Co based alloy of the above-described embodiment is used for the metal bank, the present invention is not limited to this. For example, it may be used for a member (base material).
以下に、実施例により本発明を具体的に説明するが、本発明は以下の実施例によって限定されるものではない。
（実施例１〜４、比較例１〜４）
表１に示す原料粉末を適当な配合で混合して、表２に示す組成の混合粉末を作製した。
EXAMPLES The present invention will be specifically described below with reference to examples, but the present invention is not limited to the following examples.
(Examples 1-4, Comparative Examples 1-4)
The raw material powder shown in Table 1 was mixed with an appropriate composition to prepare a mixed powder having the composition shown in Table 2.
（耐酸化性）
実施例１〜４、比較例１〜４における各インゴットから１ｃｍ角の試験片を切り出し、大気中で１０００℃、１００時間加熱した後、室温まで冷却した。次に、顕微鏡を用いて、試験片の切断面観察を行い、酸化皮膜の膜厚を測定した。
(Oxidation resistance)
A 1 cm square test piece was cut out from each ingot in Examples 1 to 4 and Comparative Examples 1 to 4, heated in the atmosphere at 1000 ° C. for 100 hours, and then cooled to room temperature. Next, the cut surface of the test piece was observed using a microscope, and the thickness of the oxide film was measured.
（平均線膨張係数）
実施例２〜４における各インゴットから長さ５０ｍｍ、断面が直径６ｍｍの円柱状の試験片を切り出し、窒素雰囲気中で２０℃から８００℃までの平均線膨張係数（以下、単に「平均線膨張係数」という）を測定した。
(Average linear expansion coefficient)
A cylindrical test piece having a length of 50 mm and a cross section of 6 mm in diameter was cut out from each ingot in Examples 2 to 4, and an average linear expansion coefficient (hereinafter simply referred to as “average linear expansion coefficient”) from 20 ° C. to 800 ° C. in a nitrogen atmosphere. ”).
（耐衝撃性）
実施例２〜４における各インゴットから長さ５５ｍｍ、断面が短辺５ｍｍ、長辺１０ｍｍの角柱状の試験片を切り出し、シャルピー衝撃試験を行った。
(Impact resistance)
A prismatic test piece having a length of 55 mm, a cross section of 5 mm, a short side of 10 mm, and a long side of 10 mm was cut out from each ingot in Examples 2 to 4, and a Charpy impact test was performed.
上記評価の結果を表３にまとめて示す。また、実施例１〜２、比較例１〜４における試験片の切断面の顕微鏡写真を図２〜図７に示す。なお、図２〜図７において、（Ａ）は熱処理前の顕微鏡写真を示し、（Ｂ）は熱処理後の顕微鏡写真を示す。 The results of the evaluation are summarized in Table 3. Moreover, the microscope picture of the cut surface of the test piece in Examples 1-2 and Comparative Examples 1-4 is shown in FIGS. 2 to 7, (A) shows a photomicrograph before heat treatment, and (B) shows a photomicrograph after heat treatment.
また、表３から明らかなように、Ｃｒ添加によって、合金の平均線膨張係数を大きくすることができ、母材の材料であるＳＵＨ３５の平均線膨張係数（１８×１０−６／℃）との差を小さくすることができた。これは、熱サイクルによって合金が割れるのを抑制できることを意味する。 Further, as is apparent from Table 3, by adding Cr, the average linear expansion coefficient of the alloy can be increased, and the average linear expansion coefficient (18 × 10 −6 / ° C.) of SUH35, which is the base material, can be increased. The difference could be reduced. This means that the alloy can be prevented from cracking due to thermal cycling.
さらに、表３から明らかなように、Ｎｉ添加によって、合金の耐衝撃性を向上することができた。 Furthermore, as is clear from Table 3, the impact resistance of the alloy could be improved by adding Ni.
１０ エンジンバルブ
１１ バルブフェース
１２ バルブシート
１３ 盛金部
１４ カム
１５ スプリング
10 Engine valve 11 Valve face 12 Valve seat 13 Depositing part 14 Cam 15 Spring
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| JP2009260468A JP2011105979A (en) | 2009-11-13 | 2009-11-13 | Mo-Co BASED ALLOY |
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| JP2009260468A JP2011105979A (en) | 2009-11-13 | 2009-11-13 | Mo-Co BASED ALLOY |
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| JP2011105979A true JP2011105979A (en) | 2011-06-02 |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2018063501A1 (en) * | 2016-09-28 | 2018-04-05 | Federal-Mogul Llc | Copper infiltrated molybdenum and/or tungsten base powder metal alloy for superior thermal conductivity |
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2009
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2018063501A1 (en) * | 2016-09-28 | 2018-04-05 | Federal-Mogul Llc | Copper infiltrated molybdenum and/or tungsten base powder metal alloy for superior thermal conductivity |
| CN109996897A (en) * | 2016-09-28 | 2019-07-09 | 天纳克公司 | The molybdenum and/or tungsten based powders metal alloy of infiltration copper with excellent heat conductivity |
| US10837087B2 (en) | 2016-09-28 | 2020-11-17 | Tenneco Inc. | Copper infiltrated molybdenum and/or tungsten base powder metal alloy for superior thermal conductivity |
| CN109996897B (en) * | 2016-09-28 | 2021-08-20 | 天纳克公司 | Copper infiltrated molybdenum and/or tungsten based powder metal alloys with excellent thermal conductivity |
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