JPS6112843A - Co base alloy for engine valve and it valve sheet - Google Patents
Co base alloy for engine valve and it valve sheetInfo
- Publication number
- JPS6112843A JPS6112843A JP13358584A JP13358584A JPS6112843A JP S6112843 A JPS6112843 A JP S6112843A JP 13358584 A JP13358584 A JP 13358584A JP 13358584 A JP13358584 A JP 13358584A JP S6112843 A JPS6112843 A JP S6112843A
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- JP
- Japan
- Prior art keywords
- engine
- remainder
- valve
- internal combustion
- further contains
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Links
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- Lift Valve (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、すぐれた高温硬さ、耐熱衝撃性、および耐
酸化鉛腐食性を有し、特にこれらの特性が要求されるが
内燃機関のエンジンバルブおよび同バルブシートの製造
に、鋳物用あるいは肉盛溶接用として使用するのに適し
たＣｏ基合金に関するものである。[Detailed Description of the Invention] [Field of Industrial Application] The present invention has excellent high-temperature hardness, thermal shock resistance, and lead oxide corrosion resistance, and is particularly applicable to internal combustion engines where these properties are required. The present invention relates to a Co-based alloy suitable for use in casting or overlay welding in the production of engine valves and valve seats.
従来、内燃機関のエンジンバルブや同バルブシートの製
造に際しては、肉盛溶接用として、アメリカ溶接協会規
格５．１３ ＲＣｏ Ｃｒ−Ａ （Ｃ： ０．９〜１
．４％、３ｉ：２．０％以下、 Ｍｎ ： １．０％
以下。Conventionally, when manufacturing engine valves and valve seats for internal combustion engines, American Welding Society standard 5.13 RCo Cr-A (C: 0.9 to 1) was used for overlay welding.
．． 4%, 3i: 2.0% or less, Mn: 1.0%
below.
Ｗ：３．０〜６．０％、Ｃｒ ： ２６〜３２％、Ｎｉ
：３．０％以下、 Ｆｅ ： ３．０％以下、 １ｙ
ｌｏ ： １．０％以下、Ｃｏおよび不・可避不純物
二残り）や、同５．１３ ＲＣｏ Ｃｒ−Ｂ （Ｃ：
１．２〜１．７％、３ｉ：２．０％以下、 １ｙｌｎ
： １．０％以下、 Ｗ ： ７．０〜９．５％
、Ｃｒ：２６〜３２％、 Ｎｉ ： ３．０％ＩＸ
下。W: 3.0-6.0%, Cr: 26-32%, Ni
: 3.0% or less, Fe: 3.0% or less, 1y
lo: 1.0% or less, Co and unavoidable impurities (remaining), 5.13 RCo Cr-B (C:
1.2-1.7%, 3i: 2.0% or less, 1yln
: 1.0% or less, W: 7.0-9.5%
, Cr: 26-32%, Ni: 3.0%IX
under.
Ｆｅ ： ３．０％以下、 １ｙｌｏ ： １．０
％以下、 ｃｏおよび不可避不純物：残り０以上重量％
）などのＣ０基合金（以下従来Ｃｏ基合金という）が多
く使用されてきた。Fe: 3.0% or less, 1ylo: 1.0
% or less, co and unavoidable impurities: remaining 0 or more weight %
) and other CO-based alloys (hereinafter referred to as conventional Co-based alloys) have been widely used.
一方、近年、内燃機関の高性能化がはかられるようにな
るにしたがって、内燃機関のエンジンバルブや同バルブ
シートにも、よりすぐれた特性を具備することが要求さ
れるようになっており、一般に、いずれも肉盛溶接６状
態で、温度８００℃におけるビッカース硬さが２８５以
上の高温硬さ、並びに温度ニア００℃に１５分間保持し
た後、水冷の操作を繰返し行なった場合に肉盛溶接部に
割れが発生するまでの前記操作回数が７回以上の耐熱衝
撃性、さらに温度二９１５℃に加熱した溶融酸化鉛中に
１時間浸漬した後の重量減が０．０９ （Ｊ／ｃｉ／ｈ
ｒ以下の耐酸化鉛腐食性を具備することが要求されるよ
うになっている。なお、これらの特性を具備することは
、鋳造により製造された内燃機関のエンジンバルブ鋳物
や同バルブシート鋳物に対しても同様に要求されること
は勿論のことである。On the other hand, as the performance of internal combustion engines has improved in recent years, engine valves and valve seats for internal combustion engines have also been required to have even better characteristics. In general, overlay welding requires high temperature hardness with a Vickers hardness of 285 or higher at a temperature of 800°C in 6 states of overlay welding, and when water cooling is repeatedly performed after holding the temperature at near 00°C for 15 minutes. Thermal shock resistance is 7 or more times before cracking occurs in the part, and the weight loss after being immersed in molten lead oxide heated to 2915°C for 1 hour is 0.09 (J/ci/ h
It is now required to have lead oxide corrosion resistance of r or less. It goes without saying that engine valve castings and valve seat castings for internal combustion engines manufactured by casting are similarly required to have these characteristics.
しかしながら、上記の従来Ｃｏ基合金は、高温硬さの点
で、上記要求条件を満足するものの、耐熱衝撃性および
耐酸化鉛腐食性については、これを満足する性質をもた
ず、したがって、高性能エンジンのエンジンバルブや同
バルブシートの製造に、前記従来Ｃｏ基合金を肉盛溶接
用として、さらに鋳物用として用いた場合に十分満足す
る使用寿命を示さないのが現状である。However, although the above-mentioned conventional Co-based alloys satisfy the above requirements in terms of high-temperature hardness, they do not have properties that satisfy these requirements in terms of thermal shock resistance and lead oxide corrosion resistance. At present, when the conventional Co-based alloy is used for overlay welding or for casting in the production of engine valves and valve seats for performance engines, it does not exhibit a sufficiently satisfactory service life.
Ｃ問題点を解決するための手段〕
そこで、本発明者等は、上述のような観点から、内燃機
関、特に高性能エンジンのエンジンバルブや同バルブシ
ートに要求される高温硬さ、耐熱衝撃性、および耐酸化
鉛腐食性を具備し、かつ肉盛溶接用および鋳物用として
使用することのできる材料を開発すべく研究を行なった
結果、Ｃ：０．５〜３．０％。Means for Solving Problem C] Therefore, from the above-mentioned viewpoint, the present inventors have developed the high-temperature hardness and thermal shock resistance required for engine valves and valve seats of internal combustion engines, particularly high-performance engines. , and lead oxide corrosion resistance, and as a result of research to develop a material that can be used for overlay welding and casting, we found that C: 0.5 to 3.0%.
Ｓｉ：３％超〜７．０％。Si: more than 3% to 7.0%.
Ｃｒ：１０〜３５％。Cr: 10-35%.
Ｗ ： ０１〜１７．０％。W: 01-17.0%.
Ｍｏ ： ０．１〜１０．０％。Mo: 0.1-10.0%.
Ｔｉ ： ０．０１〜３．０％。Ti: 0.01-3.0%.
Ａｌ ： ０．０１〜３．５％。Al: 0.01-3.5%.
を含有し、さらに必要に応じてＭｎ：０．０１ 〜２．
０％、Ｎｉ：８〜３２％、Ｆｅ：１〜１６％。and, if necessary, Mn: 0.01 to 2.
0%, Ni: 8-32%, Fe: 1-16%.
Ｎｂ ： ０．０１〜１．５０ ％オヨヒＢ ：
０．００１〜１．５０％のうちの１種または２種以上を
含有し、残りがＣｏと不可避不純物（望ましくはｃｏ＝
４０％以上含有）からなる組成（以上重量％）を有する
Ｃｏ基合金は、温度：８００℃におけるビッカース硬さ
：３１０以、トのきわめて高い高温硬さを有し、また渇
瓜ニア００℃に１５分間加熱後水冷の操作を１サイクル
とする熱ｉ撃試験で、割れ発生に至るまでのサイクル数
が９回以上のすぐれた耐熱衝撃性を示し、さらに温度二
〇１５℃に加熱した溶融酸化鉛中に１時間浸漬の酸化鉛
腐食試験では重量減が０．０２６ｇ／ ｃｒａ／ ｈ
ｒ以下のすぐれた耐酸化鉛腐食性を示し、しかも肉盛溶
接用および鋳物用としで使用することができ、したがっ
てこのＣｏ基合金を高性能エンジンバルブおよび同バル
ブシートの製造に用いた場合にきわめて長期に亘ってす
ぐれた性能を発揮するという知見を得たのである。Nb: 0.01-1.50% Oyohi B:
It contains one or more of 0.001 to 1.50%, and the rest is Co and inevitable impurities (preferably co=
A Co-based alloy having a composition (by weight) of 40% or more) has an extremely high high temperature hardness of 310 or more Vickers hardness at 800°C, and a In a thermal shock test in which one cycle was heating for 15 minutes and then cooling with water, it showed excellent thermal shock resistance with a cycle count of 9 or more until cracking occurred. In a lead oxide corrosion test immersed in lead for 1 hour, the weight loss was 0.026 g/cra/h.
It exhibits excellent lead oxide corrosion resistance of less than They have found that it exhibits excellent performance over an extremely long period of time.
この発明は、上記知見にもとづいてなされたものであっ
て、以下に成分組成を上記の通りに限定して理由を説明
する。This invention has been made based on the above knowledge, and the reason will be explained below by limiting the component composition as described above.
（ａ） Ｃ
Ｃ成分には、Ｃｒ、Ｗ、ＭＯ，ＴｉおよびＮｂなどと結
合して炭化物を形成し、常温および高温硬さを向上させ
る作用があるが、その含有量が０．５％未満では所望の
高硬度を確保することができず、一方３．０％を越えて
含有させると３ｉとの関連で耐熱衝撃性が劣化するよう
になることから、その含有量を０．５〜３．０％と定め
た。(a) C The C component combines with Cr, W, MO, Ti, Nb, etc. to form carbides and has the effect of improving hardness at room temperature and high temperature, but its content is less than 0.5%. However, if the content exceeds 3.0%, the thermal shock resistance will deteriorate in relation to 3i, so the content should be reduced to 0.5 to 3. It was set as .0%.
（ｂ） ５ｉ
Ｓｉ成分には、鋳造性、肉盛溶接性、および湯流れ性を
改善する作用があるが、その含有量が３．０％未満では
前記作用に所望の改善効果が得られず、一方７．０％を
越えて含有させてもより一層の改善効果は期待できない
ことから、その含有量を３％超〜７０％と定めた。(b) The 5i Si component has the effect of improving castability, overlay weldability, and melt flowability, but if its content is less than 3.0%, the desired improvement effect on the above effects cannot be obtained. On the other hand, even if the content exceeds 7.0%, no further improvement effect can be expected, so the content was set at more than 3% to 70%.
（ｃ） Ｃｒ
Ｃｒ成分には、その一部が素地に固溶し、残りの部分が
炭化物を形成して、特に高温硬さを向上させ、もって高
温耐摩耗性を向上させるほか、耐酸化腐食性を向上させ
る作用があるが、その含有量が１０％未満では前記作用
に所望の効果が得られず、一方３５％以上含有させると
Ｓｉとの関連で耐熱衝撃性に低下傾向が現われるように
なることから、その含有量を１０〜３５％と定めた。(c) Cr A part of the Cr component dissolves in solid solution in the base material, and the remaining part forms carbide, which particularly improves high-temperature hardness and high-temperature wear resistance, as well as oxidation and corrosion resistance. However, if the content is less than 10%, the desired effect cannot be obtained, while if the content is 35% or more, there is a tendency for thermal shock resistance to decrease in relation to Si. Therefore, the content was determined to be 10 to 35%.
（ｄ） Ｗ
Ｗ成分には、炭化物を微細化すると共に、自身も炭化物
を形成し、かつ素地に固溶して、これを強化し、もって
合金の高温硬さおよび高温強度を向上させる作用がある
が、その含有量が０．１％未満では前記作用に所望の効
果が得られず、一方１７．０％を越えて含有させると肉
盛溶接性や切削性が劣化するようになることから、その
含有量を０．１〜１７．０％と定めた。(d) W The W component has the effect of refining carbides, forming carbides themselves, and solid-dissolving them in the matrix to strengthen them, thereby improving the high-temperature hardness and high-temperature strength of the alloy. However, if the content is less than 0.1%, the desired effect cannot be obtained in the above action, while if the content exceeds 17.0%, overlay weldability and machinability will deteriorate. , its content was determined to be 0.1 to 17.0%.
（ｅ） ＭＯ
ＭＯＣ成分は、Ｗとの共存において、素地に固溶して、
これを強化し、かつ炭化物を形成して合金の高温硬さく
高温耐摩耗性）および高温強度を向上させる作用がある
が、その含有量が０１％未満では前記作用に所望の効果
が得られず、一方１０．０％を越えて含有させると、耐
熱衝撃性および靭性が劣化するようになることから、そ
の含有量を０．１〜１０，０％と定めた。(e) MO The MOC component, in coexistence with W, forms a solid solution in the base material,
It has the effect of strengthening this and forming carbides to improve the alloy's high-temperature hardness, high-temperature wear resistance) and high-temperature strength, but if its content is less than 0.1%, the desired effect cannot be obtained. On the other hand, if the content exceeds 10.0%, the thermal shock resistance and toughness will deteriorate, so the content was set at 0.1 to 10.0%.
（ｆ） Ｔｉ
Ｔｉ成分には、素地の結晶粒の成長を抑制するばかりで
なく、むしろ結晶粒を微細化し、かつ、ＭＣ型の炭化物
および窒化物、さらにＮｉおよびＡ、ｔと結合してＮｉ
３ （ＡＬ、Ｔｉ ）の金属間化合物を形成して、
高温硬さおよび耐熱ｖｊＪ撃性、さらに高温強度および
靭性を向上させる作用があるが、その含有量が０．０１
％未満では前記作用に所望の効果が得られず、一方３．
０％を越えて含有させると、炭化物の量が多くなる他、
３ｉとの関連で耐熱衝撃性および靭性が劣化するように
なるど共に、耐酸化鉛腐食性にも劣化傾向が現われるよ
うになることから、その含有量を０．０１〜３．０％と
定めた。(f) Ti The Ti component not only suppresses the growth of crystal grains in the substrate, but also refines the crystal grains and forms MC-type carbides and nitrides, as well as Ni by combining with Ni, A, and t.
3 (AL, Ti) by forming an intermetallic compound,
It has the effect of improving high temperature hardness and heat resistance vjj impact resistance, as well as high temperature strength and toughness, but its content is 0.01
If it is less than 3.%, the desired effect cannot be obtained.
If the content exceeds 0%, the amount of carbides increases, and
In connection with 3i, thermal shock resistance and toughness deteriorate, and lead oxide corrosion resistance also tends to deteriorate, so its content is set at 0.01 to 3.0%. Ta.
（（＋１ Ａｐ
Ａｌ成分には、Ｏｒと共に耐酸化鉛腐食性を向上させ、
かつ上記のようにＮｉおよびＴｉと結合してＮｉ ３
（Ａ２．Ｔｉ ）の金属間化合物を形成すると共に、
窒化物を形成して常温および高温硬さを向上させて耐摩
耗性を一段と高め、さらに耐熱衝撃性、高温強度を改善
する作用があるが、その含有量が０．０１％未満では前
記作用に所望の効果が得られず、一方３．５％を越えて
含有さＶるとＳｉ との関連で、溶接性および靭性も低
下して実用的でなくなることから、その含有量を０．０
１〜３５％と定めた。((+1 Ap Al component, along with Or, improves lead oxide corrosion resistance,
And as mentioned above, it combines with Ni and Ti to form Ni 3
While forming an intermetallic compound of (A2.Ti),
Nitride is formed to improve hardness at room temperature and high temperature, further increasing wear resistance, and further improves thermal shock resistance and high temperature strength, but if the content is less than 0.01%, the above effect is not achieved. On the other hand, if the V content exceeds 3.5%, the weldability and toughness will also decrease in relation to Si, making it impractical, so the content should be reduced to 0.0%.
It was set at 1 to 35%.
（ｈ） Ｍｎ
Ｍｎ成分には、肉盛溶接性を改善する作用があるので、
特に肉盛溶接性が要求される場合に必要に応じて含有さ
れるが、その含有量が０．０１％未満では肉盛溶接性に
所望の改善効果が得られず、一方２．０％を越えて含有
させてもより一層の改善効果は現われないことから、そ
の含有量を０．０１〜２．０％と定めた。(h) Mn Since the Mn component has the effect of improving overlay weldability,
In particular, it is contained as necessary when overlay weldability is required, but if the content is less than 0.01%, the desired improvement effect on overlay weldability cannot be obtained; Even if the content exceeds this amount, no further improvement effect will be obtained, so the content was set at 0.01 to 2.0%.
（ｉ） Ｎｉ成分には、オーステナイト地を安定にし
て耐熱衝撃性および靭性を向上させるほか、Ａｌおよび
Ｔ１と結合して金属間化合物：ＮＮ１５（Ａ、 Ｔｉ
）を形成し、もって高温硬さく高温耐摩耗性）および高
温強度を改善し、さらにＣｒとの共存において耐酸化鉛
腐食性を向上さぼる作用があるので、特にこれらの特性
が要求される場合に必要に応じて含有されるが、その含
有量が８％未満では前記作用に所望の効果が得られず、
一方３２％を越えて含有させてもより一層の向上効果は
得られないことから、その含有量を８〜３２％と定めた
。(i) The Ni component not only stabilizes the austenite base and improves thermal shock resistance and toughness, but also combines with Al and T1 to form intermetallic compounds: NN15 (A, Ti
), thereby improving high-temperature hardness, high-temperature wear resistance) and high-temperature strength, and also has the effect of improving lead oxide corrosion resistance when coexisting with Cr, so it is especially suitable when these properties are required. It is contained as necessary, but if the content is less than 8%, the desired effect cannot be obtained,
On the other hand, even if the content exceeds 32%, no further improvement effect can be obtained, so the content was set at 8 to 32%.
（ｊ） Ｆｅ
Ｆｅ成分には、合金の耐熱衝撃性を一段と向上させる作
用があるので、前記特性が要求される場合に必要に応じ
て含有されるが、その含有量が１％未満では所望の耐熱
衝撃性向上効果が得られず、一方１６％を越えて含有さ
せると、高温硬さが低下するようになることから、その
含＠量を１〜１６％と定めた。(j) Fe The Fe component has the effect of further improving the thermal shock resistance of the alloy, so it is included as necessary when the above properties are required, but if the content is less than 1%, the desired The effect of improving thermal shock resistance cannot be obtained, and on the other hand, if the content exceeds 16%, the high temperature hardness decreases, so the content was set at 1 to 16%.
（ｋ） ＮｂおよびＢ
これらの成分には高温硬さく高温耐摩耗性）および高温
強度を一段と向上させる作用があるので、特に前記作用
が要求される場合に必要に応じて含有されるが、それぞ
れ、その含有量が０．００１％未満では前記作用に所望
の向上効果が得られず、一方それぞれ１．５０％を越え
て含有させると耐熱衝撃性が劣化するようになることか
ら、それぞれの含有量を、Ｎｂ ： ０．０１〜１．
５０％、 １３ ： ０．００１〜１．５０％と定め
た。(k) Nb and B These components have the effect of further improving high-temperature hardness, high-temperature wear resistance) and high-temperature strength, so they are included as necessary when the above effects are particularly required. If the content is less than 0.001%, the desired effect of improving the above action cannot be obtained, while if the content exceeds 1.50%, the thermal shock resistance will deteriorate. The amount of Nb: 0.01 to 1.
50%, 13: 0.001 to 1.50%.
つぎに、この発明のＣｏ基合金を実施例により比較例と
対比しながら具体的に説明する。Next, the Co-based alloy of the present invention will be specifically explained using examples and comparing with comparative examples.
通常の溶解法により、それぞれ第１表に示される成分組
成をもった本発明Ｃｏｊｄ合金１〜４２、および上記の
従来Ｃｏ基合金に相当する成分組成をもった従来Ｃｏ基
合金１，２を溶製し、引続いて通常の条件にて連続鋳造
することにより直径＝４．８＃φの溶接ロンドを成形し
た。Cojd alloys 1 to 42 of the present invention, each having a composition shown in Table 1, and conventional Co-based alloys 1 and 2, each having a composition corresponding to the conventional Co-based alloy described above, were melted by a normal melting method. A welding iron having a diameter of 4.8#φ was formed by continuous casting under normal conditions.
ついで、この結果得られた本発明Ｃｏ基合金１〜４２、
および従来Ｃｏ基合金１，２の溶接ロンドを用い、ＴＩ
Ｇ自動溶接機にて、直径＝１２０ｍｍφ×厚さ：２０ｍ
ｍの寸法をもったステンレス鋼（ＳＵＳ３１６）製台金
の表面に、外径：１００ｍｍｘ幅：２０ｍｍＸ厚さ：５
ｍｍの円環状ビードを２層肉盛溶接した。Next, the resulting Co-based alloys 1 to 42 of the present invention,
and conventional welding irons of Co-based alloys 1 and 2,
Using G automatic welding machine, diameter = 120mmφ x thickness: 20m
On the surface of a stainless steel (SUS316) base metal with dimensions of m, outer diameter: 100 mm x width: 20 mm x thickness: 5
Two-layer overlay welding was performed on an annular bead with a diameter of 2 mm.
引続いて、上記台金上に形成された円環状ど−ドについ
て常温におけるロックウェル硬ざ（Ｃスケール）および
温度二８００℃におけるビツカース硬さを測定すると共
に、前記円環状ビードを形成した台金に対して、湿度＝
７００℃に加熱して１５分間保持後水冷の操作を１サイ
クルとして繰り返し行ない、前記円環状ビードに割れが
発生するまでの前記サイクル回数を測定する耐熱衝撃性
試験を行なった。さらに同様に直径＝１５Ｍφ×長ざ：
１００ｍの寸法をもったステンレス鋼片（ＳＵＳ３１６
）’に一方端面に厚さ：５ｍｍの２層肉盛溶接を行ない
、この鋼片の肉盛部より直径：１２ｍｍφ×厚さ： ’
１２ ｍｍの寸法をもった試験片を削り出し、この試験
片を用い、温度二〇１５℃に加熱した溶融酸化鉛： ４
０９中に１時間浸漬の耐酸化鉛腐食性試験を行ない、試
＠後の肉盛材の重量減を測定した。これらの測定結果を
第１表に合せて示した。Subsequently, the Rockwell hardness (C scale) at room temperature and the Vickers hardness at a temperature of 2,800°C were measured for the annular beads formed on the base metal, and the annular beads were formed on the base metal. relative to gold, humidity =
A thermal shock resistance test was conducted in which the operation of heating to 700°C, holding for 15 minutes, and then cooling with water was repeated as one cycle, and the number of cycles until cracking occurred in the annular bead was measured. Furthermore, similarly, diameter = 15Mφ x length:
Stainless steel piece (SUS316) with a dimension of 100m
)' on one end face with two layers of overlay welding with a thickness of 5 mm, and the overlay part of this steel piece has a diameter of 12 mmφ x thickness: '
A test piece with a size of 12 mm was cut out, and using this test piece, molten lead oxide was heated to a temperature of 2015°C: 4
A lead oxide corrosion resistance test was conducted by immersing the test piece in 09 water for 1 hour, and the weight loss of the overlay material after the test was measured. These measurement results are also shown in Table 1.
第１表に示される結果から、本発明Ｃｏ基合金１〜４２
は、いずれも従来Ｃｏ基合金１，２に比して一段とすぐ
れた高温硬さ、耐熱衝撃性、および耐酸化鉛腐食性を有
することが明らかである。From the results shown in Table 1, the Co-based alloys 1 to 42 of the present invention
It is clear that both have superior high-temperature hardness, thermal shock resistance, and lead oxide corrosion resistance compared to conventional Co-based alloys 1 and 2.
なお、上記実施例では、この発明のＣｏ基合金を肉盛溶
接用として用いた場合について述べたがこれを鋳物用と
して使用しても肉盛溶接の場合と同様にすぐれた特性を
示すことは勿論である。In the above example, the case where the Co-based alloy of the present invention was used for overlay welding was described, but even if it is used for casting, it will not show the same excellent characteristics as for overlay welding. Of course.
上述のように、この発明のＣｏ基合金は、高性能エンジ
ンのエンジンバルブおよび同バルブシートに要求される
上記の厳格な条件を十分余裕をもって満足するすぐれた
高温硬さ、耐熱衝撃性、および耐酸化鉛腐食性を有する
ので、これらの部材の製造に肉盛溶接用および鋳物用と
して用いた場合この結果の部材は著しく長期に亘ってす
ぐれた性能を発揮するようになるのである。As mentioned above, the Co-based alloy of the present invention has excellent high-temperature hardness, thermal shock resistance, and acid resistance that satisfies the above-mentioned strict conditions required for engine valves and valve seats for high-performance engines. Since it has lead oxide corrosive properties, when used in the manufacture of these parts for overlay welding and casting, the resulting parts exhibit excellent performance over an extremely long period of time.
Claims (1)
上重量％）を有することを特徴とする内燃機関のエンジ
ンバルブおよび同バルブシート用Ｃｏ基合金。 （２）Ｃ：０．５〜３．５％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％。 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％を含有し、
残りがＣｏと不可避不純物からなる組成（以上重量％）
を有することを特徴とする内燃機関のエンジンバルブお
よび同バルブシート用Ｃｏ基合金。 （３）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＮｉ：８〜３２％を含有し、残りがＣ
ｏと不可避不純物からなる組成（以上重量％）を有する
ことを特徴とする内燃機関のエンジンバルブおよび同バ
ルブシート用Ｃｏ基合金。 （４）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＦｅ：１〜１６％を含有し、残りがＣ
ｏと不可避不純物からなる組成（以上重量％）を有する
ことを特徴とする内燃機関のエンジンバルブおよび同バ
ルブシート用Ｃｏ基合金。 （５）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１８〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＮｂ：０．０１〜１．５０％およびＢ
：０．００１〜１．５０％のうちの１種または２種を含
有し、残りがＣｏと不可避不純物からなる組成（以上重
量％）を有することを特徴とする内燃機関のエンジンバ
ルブおよび同バルブシート用Ｃｏ基合金。 （６）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％と、Ｎｉ：
８〜３２％を含有し、残りがＣｏと不可避不純物からな
る組成（以上重量％）を有することを特徴とする内燃機
関のエンジンバルブおよび同バルブシート用Ｃｏ基合金
。 （７）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％と、Ｆｅ：
１〜１６％を含有し、残りがＣｏと不可避不純物からな
る組成（以上重量％）を有することを特徴とする内燃機
関のエンジンバルブおよび同バルブシート用Ｃｏ基合金
。 （８）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｔ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％と、Ｎｂ：
０．０１〜１．５０％およびＢ：０．０１〜１．５０％
のうちの１種または２種を含有し、残りがＣｏと不可避
不純物からなる組成（以上重量％）を有することを特徴
とする内燃機関のエンジンバルブおよび同バルブシート
用Ｃｏ基合金。 （９）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＮｉ：８〜３２％と、Ｆｅ：１〜１６
％を含有し、残りがＣｏと不可避不純物からなる組成（
以上重量％）を有することを特徴とする内燃機関のエン
ジンバルブおよび同バルブシート用Ｃｏ基合金。 （１０）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１８〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＮｉ：８〜３２％と、Ｎｂ：０．０１
〜１．５０％およびＢ：０．００１〜１．５０％のうち
の１種または２種を含有し、残りがＣｏと不可避不純物
からなる組成（以上重量％）を有することを特徴とする
内燃機関のエンジンバルブおよび同バルブシート用Ｃｏ
基合金。 （１１）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＦｅ：１〜１６％と、Ｎｂ：０．０１
〜１．５０％およびＢ：０．００１〜１．５０％のうち
の１種または２種を含有し、残りがＣｏと不可避不純物
からなる組成（以上重量％）を有することを特徴とする
内燃機関のエンジンバルブおよび同バルブシート用Ｃｏ
基合金。 （１２）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％と、Ｎｉ：
８〜３２％と、Ｆｅ：１〜１６％を含有し、残りがＣｏ
と不可避不純物からなる組成（以上重量％）を有するこ
とを特徴とする内燃機関のエンジンバルブおよび同バル
ブシート用Ｃｏ基合金。 （１３）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％と、Ｎｉ：
８〜３２％と、Ｎｂ：０．０１〜１．５０％およびＢ：
０．００１〜１．５０％のうちの１種または２種を含有
し、残りがＣｏと不可避不純物からなる組成（以上重量
％）を有することを特徴とする内燃機関のエンジンバル
ブおよび同バルブシート用Ｃｏ基合金。 （１４）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＮｉ８〜３２％と、Ｆｅ：１〜１６％
と、Ｎｂ：０．０１〜１．５０％およびＢ：０．００１
〜１．５０％のうちの１種または２種を含有し、残りが
Ｃｏと不可避不純物からなる組成（以上重量％）を有す
ることを特徴とする内燃機関のエンジンバルブおよび同
バルブシート用Ｃｏ基合（１５）Ｃ：０．５〜３．０％
、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％と、Ｆｅ：
１〜１６％と、Ｎｂ：０．０１〜１．５０％およびＢ：
０．００１〜１．５０％のうちの１種または２種を含有
し、残りがＣｏと不可避不純物からなる組成（以上重量
％）を有することを特徴とする内燃機関のエンジンバル
ブおよび同バルブシート用Ｃｏ基合金。 （１６）Ｃ：０．５〜３．０％、 Ｓｉ：３％超〜７．０％、 Ｃｒ：１０〜３５％、 Ｗ：０．１〜１７．０％、 Ｍｏ：０．１〜１０．０％、 Ｔｉ：０．０１〜３．０％、 Ａｌ：０．０１〜３．５％、 を含有し、さらにＭｎ：０．０１〜２．０％と、Ｎｉ：
８〜３２％と、Ｆｅ：１〜１６％と、Ｎｂ：０．０１〜
１．５０％およびＢ：０．００１〜１．５０％のうちの
１種または２種を含有し、残りがＣｏと不可避不純物か
らなる組成（以上重量％）を有することを特徴とする内
燃機関のエンジンバルブおよび同バルブシート用Ｃｏ基
合金。[Claims] (1) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo : 0.1 to 10.0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and the remainder is Co and inevitable impurities (weight %) A Co-based alloy for engine valves and valve seats of internal combustion engines, characterized by having the following. (2) C: 0.5 to 3.5%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%. Contains Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Mn: 0.01 to 2.0%,
Composition with the remainder consisting of Co and unavoidable impurities (more than % by weight)
A Co-based alloy for engine valves and valve seats of internal combustion engines, characterized by having the following. (3) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, further contains Ni: 8 to 32%, and the remainder is C.
A Co-based alloy for use in engine valves and valve seats of internal combustion engines, characterized by having a composition (the above weight %) consisting of o and inevitable impurities. (4) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, further contains Fe: 1 to 16%, and the remainder is C.
A Co-based alloy for use in engine valves and valve seats of internal combustion engines, characterized by having a composition (the above weight %) consisting of o and inevitable impurities. (5) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 18 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01-3.0%, Al: 0.01-3.5%, and further contains Nb: 0.01-1.50% and B
: An engine valve for an internal combustion engine, characterized in that it contains one or two of 0.001 to 1.50%, and the remainder is Co and unavoidable impurities (weight %). Co-based alloy for sheets. (6) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Mn: 0.01 to 2.0%, and Ni:
A Co-based alloy for engine valves and valve seats of internal combustion engines, characterized in that the alloy contains 8 to 32% Co, and the remainder consists of Co and unavoidable impurities (weight percent). (7) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01-3.0%, Al: 0.01-3.5%, and further contains Mn: 0.01-2.0%, Fe:
A Co-based alloy for engine valves and valve seats of internal combustion engines, characterized in that the alloy contains 1 to 16% of Co, and the remainder consists of Co and unavoidable impurities (weight percent). (8) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, At: 0.01 to 3.5%, and further contains Mn: 0.01 to 2.0%, and Nb:
0.01-1.50% and B: 0.01-1.50%
A Co-based alloy for engine valves and valve seats of internal combustion engines, characterized by containing one or two of the above, with the remainder consisting of Co and unavoidable impurities (weight percent). (9) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Ni: 8 to 32%, and Fe: 1 to 16%.
%, with the remainder consisting of Co and unavoidable impurities (
% by weight) for use in engine valves and valve seats of internal combustion engines. (10) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 18 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Ni: 8 to 32%, and Nb: 0.01
- 1.50% and B: 0.001 to 1.50%, and the remainder is Co and inevitable impurities (weight %). Co for engine engine valves and valve seats
Base alloy. (11) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Fe: 1 to 16%, and Nb: 0.01
- 1.50% and B: 0.001 to 1.50%, and the remainder is Co and inevitable impurities (weight %). Co for engine engine valves and valve seats
Base alloy. (12) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Mn: 0.01 to 2.0%, and Ni:
8 to 32%, Fe: 1 to 16%, and the remainder is Co.
A Co-based alloy for engine valves and valve seats of internal combustion engines, characterized by having a composition (the above weight %) consisting of and unavoidable impurities. (13) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Mn: 0.01 to 2.0%, and Ni:
8-32%, Nb: 0.01-1.50% and B:
An engine valve and valve seat for an internal combustion engine, characterized in that it contains one or two of 0.001 to 1.50%, with the remainder consisting of Co and unavoidable impurities (weight %). Co-based alloy. (14) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Ni 8 to 32% and Fe: 1 to 16%.
, Nb: 0.01-1.50% and B: 0.001
A Co-based material for engine valves and valve seats of internal combustion engines, characterized by containing one or two of ~1.50% and the remainder consisting of Co and unavoidable impurities (weight percent). (15)C: 0.5-3.0%
, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10.0%, Ti: 0.01 to 3.0 %, Al: 0.01 to 3.5%, further contains Mn: 0.01 to 2.0%, and Fe:
1-16%, Nb: 0.01-1.50% and B:
An engine valve for an internal combustion engine and a valve seat thereof, characterized in that the engine valve contains one or two of 0.001 to 1.50%, and the remainder is Co and inevitable impurities (weight %). Co-based alloy. (16) C: 0.5 to 3.0%, Si: more than 3% to 7.0%, Cr: 10 to 35%, W: 0.1 to 17.0%, Mo: 0.1 to 10 .0%, Ti: 0.01 to 3.0%, Al: 0.01 to 3.5%, and further contains Mn: 0.01 to 2.0%, and Ni:
8-32%, Fe: 1-16%, Nb: 0.01-
1.50% and B: 0.001 to 1.50%, and the remainder is Co and inevitable impurities (weight %). Co-based alloy for engine valves and valve seats.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13358584A JPS6112843A (en) | 1984-06-28 | 1984-06-28 | Co base alloy for engine valve and it valve sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13358584A JPS6112843A (en) | 1984-06-28 | 1984-06-28 | Co base alloy for engine valve and it valve sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6112843A true JPS6112843A (en) | 1986-01-21 |
| JPS6338415B2 JPS6338415B2 (en) | 1988-07-29 |
Family
ID=15108242
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13358584A Granted JPS6112843A (en) | 1984-06-28 | 1984-06-28 | Co base alloy for engine valve and it valve sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6112843A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6249361U (en) * | 1985-07-05 | 1987-03-26 | ||
| JPH0292495A (en) * | 1988-09-28 | 1990-04-03 | Fuji Valve Co Ltd | Wear resistant build-up welding material for engine valve |
| JPH0292496A (en) * | 1988-09-28 | 1990-04-03 | Fuji Valve Co Ltd | Wear resistant build-up welding material for engine valve |
| US6162551A (en) * | 1997-07-17 | 2000-12-19 | Daido Tokushuko Kabushiki Kaisha | Alloy used for joining to cemented carbide, and its composite material |
| CN106563863A (en) * | 2016-10-20 | 2017-04-19 | 重庆跃进机械厂有限公司 | MIG surfacing method for valve surface of air valve of medium-speed machine |
| US20190301314A1 (en) * | 2018-03-30 | 2019-10-03 | Toyota Jidosha Kabushiki Kaisha | Cladding alloy powder and assembly including the same |
-
1984
- 1984-06-28 JP JP13358584A patent/JPS6112843A/en active Granted
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6249361U (en) * | 1985-07-05 | 1987-03-26 | ||
| JPH0292495A (en) * | 1988-09-28 | 1990-04-03 | Fuji Valve Co Ltd | Wear resistant build-up welding material for engine valve |
| JPH0292496A (en) * | 1988-09-28 | 1990-04-03 | Fuji Valve Co Ltd | Wear resistant build-up welding material for engine valve |
| US6162551A (en) * | 1997-07-17 | 2000-12-19 | Daido Tokushuko Kabushiki Kaisha | Alloy used for joining to cemented carbide, and its composite material |
| CN106563863A (en) * | 2016-10-20 | 2017-04-19 | 重庆跃进机械厂有限公司 | MIG surfacing method for valve surface of air valve of medium-speed machine |
| US20190301314A1 (en) * | 2018-03-30 | 2019-10-03 | Toyota Jidosha Kabushiki Kaisha | Cladding alloy powder and assembly including the same |
| CN110315063A (en) * | 2018-03-30 | 2019-10-11 | 丰田自动车株式会社 | Alloy for surfacing powder and the component for using the alloy for surfacing powder |
| US11181014B2 (en) * | 2018-03-30 | 2021-11-23 | Toyota Jidosha Kabushiki Kaisha | Cladding alloy powder and assembly including the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6338415B2 (en) | 1988-07-29 |
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