JPH0617198A - Steel for exhaust valve excellent in high temperature strength - Google Patents
Steel for exhaust valve excellent in high temperature strengthInfo
- Publication number
- JPH0617198A JPH0617198A JP17348692A JP17348692A JPH0617198A JP H0617198 A JPH0617198 A JP H0617198A JP 17348692 A JP17348692 A JP 17348692A JP 17348692 A JP17348692 A JP 17348692A JP H0617198 A JPH0617198 A JP H0617198A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- exhaust valve
- strength
- high temperature
- temperature strength
- 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.)
- Pending
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は内燃機関の排気バルブ材
料として用いられる高温特性の優れた排気バルブ用鋼に
関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an exhaust valve steel which is used as an exhaust valve material for an internal combustion engine and has excellent high temperature characteristics.
【０００２】[0002]
【従来の技術】ガソリンエンジンおよびディーゼルエン
ジン用の排気バルブ材料としては、２１−４Ｎ (ＳＵＨ
３５ ０. ５Ｃ−９Ｍn −２１Ｃr −４Ｎi −０. ４
Ｎ) が広く使用されていた。しかし近年になってガソリ
ンエンジンの高出力化に伴い、従来よりバルブ作動温度
が上昇し、８５０℃を越すものもあり、排気バルブ材料
としては高温における強度が要求されるようになってき
た。2. Description of the Related Art Exhaust valve materials for gasoline engines and diesel engines include 21-4N (SUH
35 0.5C-9Mn -21Cr -4Ni -0.4
N) was widely used. However, in recent years, with the increase in output of gasoline engines, the valve operating temperature has risen from the past, and some have exceeded 850 ° C., and exhaust valve materials are now required to have strength at high temperatures.
【０００３】[0003]
【発明が解決しようとする課題】然るに、近年は排気バ
ルブ用鋼の常用使用温度の上昇と相まって、軽量化の要
請が強くなり、材料を細い状態で使用したいという要求
が高まり、高温強度を今までより一層向上させる必要が
生じている。However, in recent years, along with the rise in the normal use temperature of exhaust valve steel, the demand for weight reduction has become stronger, and the demand for using the material in a thin state has increased, and the high temperature strength is now increasing. There is a need for further improvement.
【０００４】かかる事情に鑑み、排気バルブ用鋼として
は、ＳＵＨ３５よりも高温疲労強度の優れたＮｉ基合
金、例えばＪＩＳ ＮＣＦ７５１等を用いて対処してい
る。したしながら、これらＮｉ基合金はＮｉを５０％以
上含有するためＳＵＨ３５に比較してコスト高である。In view of such circumstances, as a steel for an exhaust valve, a Ni-base alloy having a higher fatigue strength at high temperature than SUH35, such as JIS NCF751 is used. However, since these Ni-based alloys contain 50% or more of Ni, the cost is higher than that of SUH35.
【０００５】本発明は従来の排気バルブ用鋼が高温強度
に劣るという前記のごとき問題点を解決すべくなされた
ものであって、近年の排気バルブ用鋼の常用使用温度の
上昇と軽量化の要請に対応してＦｅ基合金として高温強
度に優れると共に併せて熱間加工性にも優れた排気バル
ブ用鋼を提供することを目的とする。The present invention has been made to solve the above-mentioned problem that conventional exhaust valve steels are inferior in high temperature strength. In recent years, exhaust gas steels have been raised in normal service temperature and reduced in weight. It is an object of the present invention to provide an exhaust valve steel excellent in high-temperature strength as an Fe-based alloy and also excellent in hot workability in response to a request.
【０００６】[0006]
【課題を解決するための手段】発明者等は排気バルブ用
鋼の高温強度を向上させることについて鋭意研究を重ね
た結果、Ｃｕを適量添加し、Ｃｕの析出強化と炭窒化物
の微細化により、高温強度が向上することを見出した。
また、強化元素のみを添加すると熱間加工性が劣化する
ので、熱間加工性にも重点をおいて、他の添加元素との
バランスについてもさらに研究を重ね、高温強度と共に
熱間加工性も従来の２１−４Ｎ並の加工性が確保される
最適含有量を見出して本発明を完成した。Means for Solving the Problems The inventors of the present invention have conducted extensive studies on improving the high temperature strength of exhaust valve steel, and as a result, by adding an appropriate amount of Cu, precipitation strengthening of Cu and refinement of carbonitride It was found that the high temperature strength was improved.
Also, if only strengthening elements are added, the hot workability deteriorates, so the hot workability is also emphasized, and further research is conducted on the balance with other additive elements to improve the hot workability as well as the high temperature strength. The present invention has been completed by finding the optimum content that ensures workability comparable to that of conventional 21-4N.
【０００７】本発明の高温強度に優れた排気バルブ用鋼
は、その第１発明として、重量比でＣ；０．４０〜０．
５５％、Ｓｉ；０．１０〜０．５０％、Ｍｎ；８．００
〜１２．００％、Ｎｉ；７．０〜１５．０％、Ｃｒ；２
０．０〜２４．０％、Ｍｏ；１．０〜４．０％、Ｃｕ；
１．５〜２．５％、Ｎ；０．３５〜０．５０％を含有
し、残部がＦｅおよび不純物元素からなることを要旨と
する。The exhaust valve steel excellent in high temperature strength of the present invention is, as the first invention, a weight ratio of C: 0.40 to 0.
55%, Si; 0.10 to 0.50%, Mn; 8.00
~ 12.00%, Ni; 7.0-15.0%, Cr; 2
0.0-24.0%, Mo; 1.0-4.0%, Cu;
The gist is that it contains 1.5 to 2.5%, N; 0.35 to 0.50%, and the balance is Fe and an impurity element.
【０００８】また、第２発明はさらに強度を向上させる
ために、第１発明にさらにＮｂ；０．０５〜１．００
％、Ｖ；０．０５〜１．００％のうち１種または２種を
含有させたものであり、第３発明はさらに熱間加工性を
改善させるために、第１発明にＭｇ；０．０００５〜
０．０２００％、Ｃａ；０．０００５〜０．０２００
％、ＲＥＭ；０．００５０〜０．０５００％、Ｂ；０．
０００５〜０．０２００％のうち１種または２種以上を
含有させたものであり、第４発明は強度と熱間加工性を
改善するため、第１発明にさらにＮｂ；０．０５〜１．
００％、Ｖ；０．０５〜１．００％のうち１種または２
種と、Ｍｇ；０．０００５〜０．０２００％、Ｃａ；
０．０００５〜０．０２００％、ＲＥＭ；０．００５０
〜０．０５００％、Ｂ；０．０００５〜０．０２００％
のうち１種または２種以上を含有させたものである。In the second invention, in order to further improve the strength, Nb; 0.05 to 1.00 is added to the first invention.
%, V; 0.05 to 1.00% of 1 type or 2 types, and the 3rd invention further improves the hot workability. 0005 ~
0.0200%, Ca; 0.0005-0.0200
%, REM; 0.0050 to 0.0500%, B; 0.
One or two or more of 0005 to 0.0200% are contained, and the fourth invention further improves strength and hot workability. Therefore, Nb; 0.05 to 1.
00%, V; 0.05 to 1.00%, 1 or 2
Seeds, Mg; 0.0005-0.0200%, Ca;
0.0005-0.0200%, REM; 0.0050
~ 0.0500%, B; 0.0005-0.0200%
Among them, one kind or two or more kinds are contained.
【０００９】[0009]
【作用】本発明の排気バルブ用鋼では、ＮｉおよびＣｒ
含有量を増加したので、耐酸化性が改善され、Ｍｏと併
せて適量のＣｕを含有させたので、Ｃｕの析出強化と炭
窒化物の微細化により高温強度と熱間加工性を向上する
ことができた。さらにＶおよびＮｂのうち１種または２
種を含有することにより、さらに高温強度が改善され、
Ｍｇ、Ｃａ、ＲＥＭ、Ｂのうち１種または２種以上を含
有することにより熱間加工性を改善することができた。In the exhaust valve steel of the present invention, Ni and Cr are used.
Since the content was increased, the oxidation resistance was improved, and since an appropriate amount of Cu was added together with Mo, the high temperature strength and hot workability should be improved by strengthening the precipitation of Cu and refining carbonitrides. I was able to. Furthermore, one or two of V and Nb
By containing the seed, the high temperature strength is further improved,
The hot workability could be improved by containing one or more of Mg, Ca, REM and B.
【００１０】次に本発明の高温強度に優れた排気バルブ
用鋼の化学成分の組成限定理由について説明する。 Ｃ；０．４０〜０．５５％ ＣはＣｒ等と炭化物を形成し鋼の高温強度を確保するた
めに必要な元素であり、この効果を得るためには少なく
とも０．４０％以上含有する必要がある。しかし、０．
５５％を越えて含有すると製造性が劣化し、耐食性およ
び溶接性が低下するので、上限を０．５５％とした。Next, the reasons for limiting the chemical composition of the exhaust valve steel of the present invention having excellent high temperature strength will be described. C: 0.40 to 0.55% C is an element necessary for forming carbides with Cr and the like to secure high temperature strength of steel, and at least 0.40% or more is necessary to obtain this effect. There is. However, 0.
If the content exceeds 55%, the manufacturability is deteriorated and the corrosion resistance and the weldability are deteriorated, so the upper limit was made 0.55%.
【００１１】Ｓｉ；０．１０〜０．５０％ Ｓｉは溶解時に必要な脱酸をするために添加される元素
であり、前記効果を得るためには少なくとも０．１０％
以上含有させる必要がある。しかし、０．５０％を越え
て含有させると靱性が低下しクリープ破断強度が低下す
るので、上限を０．５０％とした。Si: 0.10 to 0.50% Si is an element added for deoxidation necessary for melting, and at least 0.10% to obtain the above effect.
It is necessary to contain the above. However, if the content exceeds 0.50%, the toughness decreases and the creep rupture strength decreases, so the upper limit was made 0.50%.
【００１２】Ｍｎ；８．０〜１２．０％ Ｍｎはオーステナイト組織を安定化し、ＭｎＳとしてＳ
を固定し熱間脆性防止に役立つ元素である。前記効果を
得るためには８．０％以上含有させる必要がある。しか
し１２．０％を越えて含有させると、靱性および延性が
低下し、耐酸化性が劣化するので、上限を１２．０％と
した。Mn: 8.0-12.0% Mn stabilizes the austenite structure and becomes S as MnS.
It is an element that fixes and fixes hot brittleness. In order to obtain the above effect, it is necessary to contain 8.0% or more. However, if the content exceeds 12.0%, the toughness and ductility decrease and the oxidation resistance deteriorates, so the upper limit was made 12.0%.
【００１３】Ｎｉ；７．０〜１５．０％ Ｎｉはオーステナイト相を安定化するために必須の成分
であり、また耐熱性および耐酸化性を確保するために必
要な元素である。前記効果を確保するためには少なくと
も７．０％以上含有させる必要がある。しかし、１５．
０％を越えて含有させても前記効果が飽和すると共に、
原価が高くなるので、上限を１５．０％とした。Ni: 7.0 to 15.0% Ni is an essential component for stabilizing the austenite phase, and is an element necessary for ensuring heat resistance and oxidation resistance. In order to secure the above effect, it is necessary to contain at least 7.0% or more. However, 15.
Even if the content exceeds 0%, the above effect is saturated and
Since the cost is high, the upper limit was set to 15.0%.
【００１４】Ｃｒ：２０．０〜２４．０％ Ｃｒは炭窒化物を形成し耐食性を確保するために必要な
元素であり、この効果を得るためには２０．０％以上含
有させる必要がある。しかし、２４．０％を越えて含有
させると、σ相を生成し靱性および延性を低下し、クリ
ープ破断強度を劣化するので、上限を２４．０％とし
た。Cr: 20.0 to 24.0% Cr is an element necessary for forming carbonitrides and ensuring corrosion resistance, and in order to obtain this effect, it is necessary to contain 20.0% or more. . However, if the content exceeds 24.0%, a σ phase is generated, the toughness and ductility are reduced, and the creep rupture strength is deteriorated, so the upper limit was made 24.0%.
【００１５】Ｍｏ；１．０〜４．０％ Ｍｏは生地に固溶して固溶強化するので、クリープ破断
強度を向上するために必要な元素である。前記効果を得
るためには、１．０％以上の含有が必要である。しか
し、４．０％を越えて含有させても前記効果が飽和する
と共に、耐酸化性を損ない、また熱間加工性が劣化する
ので、上限を４．０％とした。Mo: 1.0 to 4.0% Mo is a necessary element for improving creep rupture strength because it forms a solid solution in the base material to strengthen it. In order to obtain the above effect, the content of 1.0% or more is required. However, when the content exceeds 4.0%, the above effect is saturated, the oxidation resistance is impaired, and the hot workability is deteriorated, so the upper limit was made 4.0%.
【００１６】Ｃｕ；１．５〜２．５％ Ｃｕは高温引張強度およびクリープ破断強度を向上させ
るために必要な元素であり、この効果を得るためには少
なくとも１．５％以上含有させることが必要である。し
かし、２．５％を越えて含有させると、熱間加工性を劣
化し、高温強度を低下させるので、上限を２．５％とし
た。Cu: 1.5 to 2.5% Cu is an element necessary for improving high temperature tensile strength and creep rupture strength, and in order to obtain this effect, it is necessary to contain at least 1.5% or more. is necessary. However, if the content exceeds 2.5%, the hot workability deteriorates and the high temperature strength decreases, so the upper limit was made 2.5%.
【００１７】Ｎ；０．３５〜０．５０％ ＮはＣｒと窒化物を形成しクリープ強度を向上させる元
素であり、この効果を得るためには少なくとも０．３５
％以上を含有する必要がある。しかし、０．５０％を越
えて含有させると、製造性が劣化すると共に耐食性およ
び溶接性が低下するので、上限を０．５０％とした。N: 0.35 to 0.50% N is an element that forms a nitride with Cr to improve creep strength, and at least 0.35 is required to obtain this effect.
% Must be contained. However, if the content exceeds 0.50%, the manufacturability deteriorates and the corrosion resistance and weldability deteriorate, so the upper limit was made 0.50%.
【００１８】Ｎｂ；０．０５〜１．００％、Ｖ；０．０
５〜１．００％のうち１種または２種ＶおよびＮｂは炭
窒化物を形成して高温強度を改善するため、０．０５％
以上の含有が必要である。しかし、１．００％以上含有
させても、前記効果が飽和すると共に原価高となるの
で、上限を１．００％とした。Nb: 0.05 to 1.00%, V: 0.0
5 to 1.00% of 1 or 2 V and Nb form carbonitrides to improve high temperature strength, so 0.05%
The above contents are required. However, even if it is contained in an amount of 1.00% or more, the above effect is saturated and the cost becomes high, so the upper limit was made 1.00%.
【００１９】Ｍｇ；０．０００５〜０．０２００％、Ｃ
ａ；０．０００５〜０．０２００％、ＲＥＭ；０．００
５０〜０．０５００％、Ｂ；０．０００５〜０．０２０
０％のうち１種または２種以上Ｂ、Ｃａ、ＭｇおよびＲ
ＥＭは熱間加工性を改善するために必要な元素で、この
効果を得るためには、Ｂ、Ｃａ、Ｍｇについては０．０
００５％以上、ＲＥＭについては０．００５０％以上の
含有が必要である。しかし、多量に含有させると却って
熱間加工性を劣化させるので、Ｂ、Ｃａ、Ｍｇについて
は０．０２００％、ＲＥＭについては０．０５００％を
上限とした。Mg: 0.0005 to 0.0200%, C
a; 0.0005 to 0.0200%, REM; 0.00
50-0.0500%, B; 0.0005-0.020
One or more of 0% B, Ca, Mg and R
EM is an element necessary for improving hot workability. To obtain this effect, B, Ca, and Mg are 0.0
005% or more, and REM needs to be 0.0050% or more. However, if it is contained in a large amount, the hot workability is rather deteriorated. Therefore, 0.0200% for B, Ca and Mg and 0.0500% for REM were set as the upper limits.
【００２０】[0020]
【実施例】本発明の実施例を比較例および従来例と比較
しつつ説明し、本発明の特徴を明らかにする。表１に示
す化学成分からなる本発明鋼、比較鋼および従来鋼を電
気炉にて溶製した。表１において、１〜１２鋼は本発明
例であって、１〜３鋼は第１発明、４〜６鋼は第２発
明、７〜９鋼は第３発明、１０〜１２鋼は第４発明であ
る。１３〜１７鋼は比較鋼であって、１３鋼はＣｕ含有
量が本発明の組成範囲より高い比較鋼、１４鋼はＣｕ含
有量が本発明の組成範囲より低い比較鋼、１５鋼はＭｏ
含有量が本発明の組成範囲より多い比較鋼、１６鋼はＭ
ｏ含有量が本発明の組成範囲より低い比較鋼、１７鋼は
Ｃ含有量が本発明の組成範囲より高い比較鋼である。ま
た、１８鋼はＳＵＨ３５に相当する成分の従来鋼であ
る。EXAMPLES Examples of the present invention will be described in comparison with comparative examples and conventional examples to clarify the features of the present invention. Inventive steels, comparative steels and conventional steels having the chemical compositions shown in Table 1 were melted in an electric furnace. In Table 1, 1 to 12 steels are examples of the present invention, 1 to 3 steels are 1st inventions, 4 to 6 steels are 2nd inventions, 7 to 9 steels are 3rd inventions, and 10 to 12 steels are 4th inventions. It is an invention. Steels 13 to 17 are comparative steels, steel 13 is a comparative steel having a Cu content higher than the composition range of the present invention, steel 14 is a comparative steel having a Cu content lower than the composition range of the present invention, and steel 15 is Mo.
Comparative steels with a content higher than the composition range of the present invention, 16 steels are M
Comparative steels having an o content lower than the composition range of the present invention, and steel 17 are comparative steels having a C content higher than the composition range of the present invention. Further, 18 steel is a conventional steel having a composition corresponding to SUH35.
【００２１】[0021]
【表１】 [Table 1]
【００２２】表１に示す各鋼について鍛造後１１００℃
で４５分間固溶化熱処理を施したのち水冷し、ついで７
５０℃で４時間時効処理を施した。続いて、各鋼につい
て、高温引張強さ、クリープ強度および熱間加工性につ
いて測定した。For each steel shown in Table 1, 1100 ° C. after forging
After solid solution heat treatment for 45 minutes, cool with water and then 7
Aging treatment was performed at 50 ° C. for 4 hours. Subsequently, the high temperature tensile strength, creep strength and hot workability of each steel were measured.
【００２３】高温引張強さについては、平行部直径５m
m、平行部長さ２５mmの試験片を用いて９００℃におい
て引張強さを測定した。クリープ試験は直径６mmの試験
片を用い試験温度８５０℃、１００時間のクリープ破断
強度を測定した。熱間加工性については、９００℃、１
０００℃および１１００℃でグリーブルによって引張試
験を行い、その絞り値を測定した。得られた結果は表２
に併せて示した。Regarding high temperature tensile strength, the diameter of the parallel part is 5 m
Tensile strength was measured at 900 ° C. using a test piece having m and a parallel part length of 25 mm. In the creep test, a test piece having a diameter of 6 mm was used to measure the creep rupture strength at a test temperature of 850 ° C. for 100 hours. For hot workability, 900 ℃, 1
Tensile test was conducted by gleable at 000 ° C. and 1100 ° C., and the aperture value was measured. The results obtained are shown in Table 2.
Are also shown.
【００２４】[0024]
【表２】 [Table 2]
【００２５】表２に示したように、１３鋼のＣｕ含有量
が本発明の組成範囲より高い比較鋼は、クリープ強度が
５．９ｋｇｆ／ｍｍ2と低い上に、グリーブル絞り値が
低く熱間加工性に劣り、１４鋼のＣｕ含有量が本発明の
組成範囲より低い比較鋼は、高温引張強度が２２．３ｋ
ｇｆ／ｍｍ2と低い上にグリーブル絞り値が低く熱間加
工性に劣った。また、１５鋼のＭｏ含有量が本発明の組
成範囲より多い比較鋼は、グリーブル絞り値が低く熱間
加工性に劣り、１６鋼のＭｏ含有量が本発明の組成範囲
より低い比較鋼はクリープ強度および高温強度等の高温
特性において劣った。１７鋼のＣ含有量が本発明の組成
範囲より高い比較鋼は、グリーブル絞り値が低く熱間加
工性に劣った。なお、１８鋼の従来鋼のクリープ強度は
４．２ｋｇｆ／ｍｍ2、高温強度は１８．９ｋｇｆ／ｍ
ｍ2であった。As shown in Table 2, the comparative steels in which the Cu content of the 13th steel is higher than the composition range of the present invention have a low creep strength of 5.9 kgf / mm 2 and a low greeble drawing value and a hot workability. Comparative steels having poor workability and having a Cu content of 14 steel lower than the composition range of the present invention had a high temperature tensile strength of 22.3 k.
It had a low gf / mm 2 and a low greeble drawing value, resulting in poor hot workability. Further, the comparative steels in which the Mo content of the 15th steel is more than the composition range of the present invention have a low greeble drawing value and poor hot workability, and the comparative steels in which the Mo content of the 16th steel is lower than the composition range of the present invention creep It was inferior in high temperature characteristics such as strength and high temperature strength. Comparative steels in which the C content of the 17th steel was higher than the composition range of the present invention had a low greeble drawing value and poor hot workability. In addition, the creep strength of the conventional 18 steel is 4.2 kgf / mm 2 , and the high temperature strength is 18.9 kgf / m 2.
It was m 2 .
【００２６】これに対して、本発明鋼である１〜１２鋼
はクリープ強度が６. ２〜７．６ｋｇｆ／ｍｍ2、高温
引張強さが２３．２〜２６．０ｋｇｆ／ｍｍ2であって
高温特性に優れ、またグリーブル絞りは９００℃で６３
〜７２％、１０００℃で８０〜８６％、１１００℃で９
０〜９５％であって熱間加工性も従来鋼と同等かそれ以
上であり、本発明の効果が確認された。On the other hand, the steels 1 to 12 of the present invention have a creep strength of 6.2 to 7.6 kgf / mm 2 and a high temperature tensile strength of 23.2 to 26.0 kgf / mm 2. It has excellent high temperature characteristics, and the greeble diaphragm is 63
~ 72%, 80-86% at 1000 ° C, 9 at 1100 ° C
The hot workability was 0 to 95%, which was equal to or higher than that of the conventional steel, and the effect of the present invention was confirmed.
【００２７】[0027]
【発明の効果】本発明の排気バルブ用鋼は、以上説明し
たように、Ｎｉ、Ｍｏと併せて適量のＣｕを含有させた
ので、Ｃｕの析出強化と炭窒化物の微細化により高温強
度と熱間加工性を向上することができ、８５０℃１００
時間クリープ破断強度が６．２ｋｇｆ／ｍｍ2以上、９
００℃引張強さが２３．２ｋｇｆ／ｍｍ2以上と高温特
性に優れ、グリーブル絞り値も１０００℃で８０％以上
で従来鋼と同等の熱間加工性が確保され、内燃機関の排
気バルブ用材料として極めて有用である。As described above, the steel for exhaust valves of the present invention contains an appropriate amount of Cu in addition to Ni and Mo. Therefore, precipitation strengthening of Cu and refinement of carbonitrides lead to high temperature strength. Can improve hot workability, 850 ℃ 100
Time creep rupture strength is 6.2 kgf / mm 2 or more, 9
It has excellent high-temperature characteristics with a tensile strength of 00 ° C of 23.2 kgf / mm 2 or more, and a greeble drawing value of 80% or more at 1000 ° C, ensuring hot workability equivalent to that of conventional steel, and a material for exhaust valves of internal combustion engines. Is extremely useful as
Claims (4)
ｉ；０．１０〜０．５０％、Ｍｎ；８．００〜１２．０
０％、Ｎｉ；７．０〜１５．０％、Ｃｒ；２０．０〜２
４．０％、Ｍｏ；１．０〜４．０％、Ｃｕ；１．５〜
２．５％、Ｎ；０．３５〜０．５０％を含有し、残部が
Ｆｅおよび不純物元素からなることを特徴とする高温強
度に優れた排気バルブ用鋼。1. C: 0.40 to 0.55% by weight, S
i; 0.10 to 0.50%, Mn; 8.00 to 12.0
0%, Ni; 7.0-15.0%, Cr; 20.0-2
4.0%, Mo; 1.0 to 4.0%, Cu; 1.5 to
Exhaust valve steel excellent in high-temperature strength, characterized in that it contains 2.5%, N; 0.35 to 0.50%, and the balance is Fe and impurity elements.
ｉ；０．１０〜０．５０％、Ｍｎ；８．００〜１２．０
０％、Ｎｉ；７．０〜１５．０％、Ｃｒ；２０．０〜２
４．０％、Ｍｏ；１．０〜４．０％、Ｃｕ；１．５〜
２．５％、Ｎ；０．３５〜０．５０％を含有し、さらに
Ｎｂ；０．０５〜１．００％、Ｖ；０．０５〜１．００
％のうち１種または２種を含有し、残部がＦｅおよび不
純物元素からなることを特徴とする高温強度に優れた排
気バルブ用鋼。2. A weight ratio of C; 0.40 to 0.55%, S
i; 0.10 to 0.50%, Mn; 8.00 to 12.0
0%, Ni; 7.0-15.0%, Cr; 20.0-2
4.0%, Mo; 1.0 to 4.0%, Cu; 1.5 to
2.5%, N: 0.35 to 0.50%, and Nb: 0.05 to 1.00%, V: 0.05 to 1.00
%, And the balance is Fe and an impurity element, and the exhaust valve steel is excellent in high-temperature strength.
ｉ；０．１０〜０．５０％、Ｍｎ；８．００〜１２．０
０％、Ｎｉ；７．０〜１５．０％、Ｃｒ；２０．０〜２
４．０％、Ｍｏ；１．０〜４．０％、Ｃｕ；１．５〜
２．５％、Ｎ；０．３５〜０．５０％を含有し、さらに
Ｍｇ；０．０００５〜０．０２００％、Ｃａ；０．００
０５〜０．０２００％、ＲＥＭ；０．００５０〜０．０
５００％、Ｂ；０．０００５〜０．０２００％のうち１
種または２種以上を含有し、残部がＦｅおよび不純物元
素からなることを特徴とする高温強度に優れた排気バル
ブ用鋼。3. C: 0.40 to 0.55% by weight, S
i; 0.10 to 0.50%, Mn; 8.00 to 12.0
0%, Ni; 7.0-15.0%, Cr; 20.0-2
4.0%, Mo; 1.0 to 4.0%, Cu; 1.5 to
2.5%, N: 0.35 to 0.50%, Mg: 0.0005 to 0.0200%, Ca: 0.00
05-0.0200%, REM; 0.0050-0.0
500%, B; 1 out of 0.0005 to 0.0200%
Exhaust valve steel excellent in high-temperature strength, characterized in that it contains one or more kinds, and the balance is Fe and impurity elements.
ｉ；０．１０〜０．５０％、Ｍｎ；８．００〜１２．０
０％、Ｎｉ；７．０〜１５．０％、Ｃｒ；２０．０〜２
４．０％、Ｍｏ；１．０〜４．０％、Ｃｕ；１．５〜
２．５％、Ｎ；０．３５〜０．５０％を含有し、さらに
Ｎｂ；０．０５〜１．００％、Ｖ；０．０５〜１．００
％のうち１種または２種と、Ｍｇ；０．０００５〜０．
０２００％、Ｃａ；０．０００５〜０．０２００％、Ｒ
ＥＭ；０．００５０〜０．０５００％、Ｂ；０．０００
５〜０．０２００％のうち１種または２種以上を含有
し、残部がＦｅおよび不純物元素からなることを特徴と
する高温強度に優れた排気バルブ用鋼。4. C: 0.40 to 0.55% by weight, S
i; 0.10 to 0.50%, Mn; 8.00 to 12.0
0%, Ni; 7.0-15.0%, Cr; 20.0-2
4.0%, Mo; 1.0 to 4.0%, Cu; 1.5 to
2.5%, N: 0.35 to 0.50%, and Nb: 0.05 to 1.00%, V: 0.05 to 1.00
%, One or two of Mg; 0.0005 to 0.
0200%, Ca; 0.0005-0.0200%, R
EM; 0.0050 to 0.0500%, B; 0.000
Exhaust valve steel excellent in high-temperature strength, characterized by containing one or more of 5 to 0.0200% and the balance being Fe and impurity elements.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17348692A JPH0617198A (en) | 1992-06-30 | 1992-06-30 | Steel for exhaust valve excellent in high temperature strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17348692A JPH0617198A (en) | 1992-06-30 | 1992-06-30 | Steel for exhaust valve excellent in high temperature strength |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0617198A true JPH0617198A (en) | 1994-01-25 |
Family
ID=15961401
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17348692A Pending JPH0617198A (en) | 1992-06-30 | 1992-06-30 | Steel for exhaust valve excellent in high temperature strength |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0617198A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5753179A (en) * | 1996-05-20 | 1998-05-19 | Tohoku Steel Co., Ltd. | Steels for exhaust valves having improved fatigue strength at high temperature, corrosion resistance at room and higher temperatures and oxidation resistance |
| JP2002294411A (en) * | 2001-03-29 | 2002-10-09 | Tohoku Tokushuko Kk | Steel for exhaust vale high in high-temperature strength and superior in resistances to corrosion and abrasion |
| CN100450651C (en) * | 2007-04-04 | 2009-01-14 | 江苏申源特钢有限公司 | Method for producing cogging by air-valve steel rolling |
| WO2013027841A1 (en) * | 2011-08-24 | 2013-02-28 | 大同特殊鋼株式会社 | Heat-resisting steel for exhaust valves |
| CN110616380A (en) * | 2018-06-20 | 2019-12-27 | 无锡市东明冠特种金属制造有限公司 | Non-magnetic martensite and preparation method thereof |
| WO2023067317A1 (en) * | 2021-10-18 | 2023-04-27 | Alloyed Limited | A heat-resistant austenitic stainless steel |
-
1992
- 1992-06-30 JP JP17348692A patent/JPH0617198A/en active Pending
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5753179A (en) * | 1996-05-20 | 1998-05-19 | Tohoku Steel Co., Ltd. | Steels for exhaust valves having improved fatigue strength at high temperature, corrosion resistance at room and higher temperatures and oxidation resistance |
| JP2002294411A (en) * | 2001-03-29 | 2002-10-09 | Tohoku Tokushuko Kk | Steel for exhaust vale high in high-temperature strength and superior in resistances to corrosion and abrasion |
| CN100450651C (en) * | 2007-04-04 | 2009-01-14 | 江苏申源特钢有限公司 | Method for producing cogging by air-valve steel rolling |
| WO2013027841A1 (en) * | 2011-08-24 | 2013-02-28 | 大同特殊鋼株式会社 | Heat-resisting steel for exhaust valves |
| CN103764861A (en) * | 2011-08-24 | 2014-04-30 | 大同特殊钢株式会社 | Heat-resisting steel for exhaust valves |
| EP2749663A4 (en) * | 2011-08-24 | 2016-02-24 | Daido Steel Co Ltd | Heat-resisting steel for exhaust valves |
| US9745649B2 (en) | 2011-08-24 | 2017-08-29 | Daido Steel Co., Ltd. | Heat-resisting steel for exhaust valves |
| CN110616380A (en) * | 2018-06-20 | 2019-12-27 | 无锡市东明冠特种金属制造有限公司 | Non-magnetic martensite and preparation method thereof |
| WO2023067317A1 (en) * | 2021-10-18 | 2023-04-27 | Alloyed Limited | A heat-resistant austenitic stainless steel |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP0016225B1 (en) | Use of an austenitic steel in oxidizing conditions at high temperature | |
| JP4830466B2 (en) | Heat-resistant alloy for exhaust valves that can withstand use at 900 ° C and exhaust valves using the alloys | |
| JP4197492B2 (en) | Ferritic stainless steel for exhaust gas flow path members | |
| JP5137934B2 (en) | Ferritic heat resistant steel | |
| EP1004685A2 (en) | Heat-resisting cast steel | |
| JP3543366B2 (en) | Austenitic heat-resistant steel with good high-temperature strength | |
| US4631169A (en) | Alloys for exhaust valves | |
| JPS6250542B2 (en) | ||
| WO1994026947A1 (en) | High-strength austenitic heat-resisting steel with excellent weldability and good high-temperature corrosion resistance | |
| JPH0617198A (en) | Steel for exhaust valve excellent in high temperature strength | |
| JPWO2010150795A1 (en) | Heat resistant steel for engine valves with excellent high temperature strength | |
| JPH07331390A (en) | High chromium austenitic heat resistant alloy | |
| JP3388998B2 (en) | High strength austenitic heat-resistant steel with excellent weldability | |
| JPS6123749A (en) | Austenitic stainless steel having high strength at high temperature | |
| JPH07138708A (en) | Austenitic steel good in high temperature strength and hot workability | |
| JP2002167655A (en) | Stainless cast steel having excellent heat resistance and machinability | |
| JP3424314B2 (en) | Heat resistant steel | |
| JP2716807B2 (en) | High strength low alloy heat resistant steel | |
| JP2561592B2 (en) | Welding material for high Cr ferritic heat resistant steel | |
| JP2863583B2 (en) | Cr-Ni heat-resistant steel | |
| JPH03285050A (en) | Exhaust valve steel excellent in high temperature characteristic | |
| JP3177633B2 (en) | Extremely low Mn and low Cr ferrite heat resistant steel with excellent high temperature strength | |
| JP2004292868A (en) | Inexpensive austenitic heat resistant cast steel having satisfactory castability, high temperature strength and oxidation resistance, and exhaust system component obtained by using the same | |
| JP3565155B2 (en) | High strength low alloy heat resistant steel | |
| JP5239644B2 (en) | Ferritic stainless steel with excellent thermal fatigue properties, high temperature fatigue properties, oxidation resistance and toughness |