JP3283088B2 - Machine structural parts with excellent fatigue strength - Google Patents
Machine structural parts with excellent fatigue strengthInfo
- Publication number
- JP3283088B2 JP3283088B2 JP04938493A JP4938493A JP3283088B2 JP 3283088 B2 JP3283088 B2 JP 3283088B2 JP 04938493 A JP04938493 A JP 04938493A JP 4938493 A JP4938493 A JP 4938493A JP 3283088 B2 JP3283088 B2 JP 3283088B2
- Authority
- JP
- Japan
- Prior art keywords
- nitriding
- fatigue strength
- less
- steel
- excellent fatigue
- 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.)
- Expired - Lifetime
Links
- 229910000831 Steel Inorganic materials 0.000 claims description 17
- 239000010959 steel Substances 0.000 claims description 17
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 150000004767 nitrides Chemical class 0.000 claims 1
- 238000005121 nitriding Methods 0.000 description 41
- 238000000034 method Methods 0.000 description 11
- 230000000694 effects Effects 0.000 description 7
- 239000011651 chromium Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- 238000009661 fatigue test Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 229910019582 Cr V Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- VNTLIPZTSJSULJ-UHFFFAOYSA-N chromium molybdenum Chemical compound [Cr].[Mo] VNTLIPZTSJSULJ-UHFFFAOYSA-N 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000010606 normalization Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、各種機械構造部品に用
いられる窒化用鋼、特に疲労強度特性に優れた窒化用鋼
に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a nitriding steel used for various mechanical structural parts, and more particularly to a nitriding steel having excellent fatigue strength characteristics.
【０００２】[0002]
【従来の技術及び発明が解決しようとする課題】機械構
造用鋼の疲労強度向上のための表面硬化処理方法の一つ
としてガス窒化処理がある。このガス窒化処理は同じ表
面硬化処理方法である高周波焼入れや浸炭焼入れに比べ
て熱処理歪が小さいため、有効な表面硬化処理法として
広く利用されている。2. Description of the Related Art As one of the surface hardening methods for improving the fatigue strength of steel for machine structural use, there is a gas nitriding treatment. This gas nitriding treatment is widely used as an effective surface hardening method because it has less heat treatment distortion than induction hardening or carburizing quenching which is the same surface hardening method.
【０００３】窒化処理用鋼材としては、一般的には、機
械構造用炭素鋼（ＪＩＳＧ４０５１）やクロムモリブデ
ン鋼（ＪＩＳＧ４１０５）が用いられるが、アルミニウ
ム・クロム・モリブデン鋼（ＪＩＳＧ４２０２）のよう
な窒化用鋼が用いられる場合もある。しかし、いずれの
鋼種も、一般的なガス窒化処理では硬化深さが浅く、疲
労強度も低いという問題点があった。[0003] As a steel material for nitriding treatment, carbon steel for machine structure (JIS G4051) or chromium molybdenum steel (JIS G4105) is generally used. Is sometimes used. However, all of the steel types have a problem that the depth of hardening is small and the fatigue strength is low by general gas nitriding.
【０００４】これらに対して特開平４−４５２４４号公
報や特公昭５５−３１１６８号公報では、Ｃｒ−Ｖ添加
鋼に通常の窒化処理を行なって、表面硬さ及び有効硬化
深さの向上を計っているが、有効硬化深さは０．２〜
０．３５ｍｍと浅く、疲労強度も十分とは言い難い。On the other hand, in JP-A-4-45244 and JP-B-55-31168, ordinary nitriding treatment is performed on Cr-V added steel to improve the surface hardness and the effective hardening depth. But the effective hardening depth is 0.2 ~
It is as shallow as 0.35 mm, and the fatigue strength is hardly sufficient.
【０００５】本発明は、かかる事情に鑑みてなされたも
のであって、０．４ｍｍ以上の有効硬化深さを得ること
ができ、疲労強度に優れた窒化用鋼を得ることを目的と
する。The present invention has been made in view of such circumstances, and an object of the present invention is to obtain a nitriding steel having an effective hardening depth of 0.4 mm or more and having excellent fatigue strength.
【０００６】[0006]
【課題を解決するための手段及び作用】本発明は鋼成分
が重量％で、Ｃ：０．２５％超え、０．４５％以下，Ｓ
ｉ：０．０５〜１．０％、Ｍｎ：０．１〜１．０％、
Ｓ：０．１０％以下、Ｃｒ：０．５〜２．０％、Ｍｏ：
１．５〜２．５％、Ｖ：０．０５％以上、０．２％未
満、Ａｌ：０．０５％以下を含有し、残部がＦｅ及び不
可避的不純物からなり、窒化処理による有効硬化深さが
０．４ｍｍ以上、表面硬度Ｈｖ７００〜８００を特徴と
する疲労強度に優れた機械構造部品を提供する。 According to the present invention, the steel component is expressed by weight%, and C: more than 0.25% and less than 0.45%, S
i: 0.05 to 1.0%, Mn: 0.1 to 1.0%,
S: 0.10% or less, Cr: 0.5 to 2.0%, Mo:
1.5 to 2.5%, V: 0.05% or more, less than 0.2%, Al: 0.05% or less, the balance being Fe and unavoidable impurities, the effective hardening depth by nitriding treatment Saga
0.4mm or more, characterized by surface hardness Hv700-800
To provide mechanical structural parts having excellent fatigue strength.
【０００７】本願発明者らは、大きな有効深さを得るこ
とができ、優れた疲労強度を有する窒化用鋼を得るべく
鋭意研究を行った結果、１）Ｃ量を一定範囲に制限し、
Ｃｒ及びＶと共にＭｏを多量に添加したＣｒ−Ｖ−Ｍｏ
添加鋼を基本とすることにより、０．４ｍｍ以上の大き
な有効硬化深さを得ることができること、及び２）優れ
た疲労強度を得る観点からは表面硬さをＨＶ７００〜８
００に抑制する必要があり、そのためにはＡｌの添加を
抑制することが有効であることを見出した。上記構成を
有する本発明は、本願発明者らのこのような知見に基づ
いてなされたものである。以下、本発明について詳細に
説明する。先ず、成分限定範囲とその限定理由を示す。
なお、以下に示す％表示は、いずれも重量％を示すもの
である。[0007] The inventors of the present application have conducted intensive studies to obtain a nitrided steel having a large effective depth and excellent fatigue strength. As a result, 1) limiting the C content to a certain range;
Cr-V-Mo with a large amount of Mo added together with Cr and V
By using the added steel as a base, a large effective hardening depth of 0.4 mm or more can be obtained, and 2) From the viewpoint of obtaining excellent fatigue strength, the surface hardness is HV700 to HV8.
It has been found that it is effective to suppress the addition of Al to achieve this. The present invention having the above-described configuration has been made based on such findings of the present inventors. Hereinafter, the present invention will be described in detail. First, the component limitation range and the reason for limitation are shown.
The percentages shown below are all percentages by weight.
【０００８】Ｃ：強度確保のため必要な元素であり、ま
た有効硬化深さに影響する元素であって、これらの観点
から０．２５％を超えることが必要である。しかし、そ
の量が０．４５％を超えると靱性が低下する。従ってＣ
含有量を０．２５％超え、０．４５％以下の範囲に規定
する。C: an element necessary for securing the strength and an element that affects the effective hardening depth. From these viewpoints, it is necessary to exceed 0.25%. However, if the amount exceeds 0.45%, the toughness decreases. Therefore C
The content is specified in the range of more than 0.25% and 0.45% or less.
【０００９】Ｓｉ：脱酸に必要であるとともに強度確保
に必要な元素であるが、０．０５％未満では所望の効果
が得られない。一方、その量が１．０％を超えると靱性
が低下する。従ってＳｉ含有量を０．０５〜１．０％の
範囲に規定する。[0009] Si: an element necessary for deoxidation and necessary for securing strength, if less than 0.05%, desired effects cannot be obtained. On the other hand, if the amount exceeds 1.0%, the toughness decreases. Therefore, the Si content is defined in the range of 0.05 to 1.0%.
【００１０】Ｍｎ：強度確保のため必要な元素である
が、０．１％未満では必要な強度が得られない。一方、
その量が１．０％を超えると靱性が低下する。従ってＭ
ｎ含有量を０．１〜１．０％の範囲に規定する。Mn: Necessary element for securing strength, but if less than 0.1%, required strength cannot be obtained. on the other hand,
If the amount exceeds 1.0%, the toughness decreases. Therefore M
The n content is specified in the range of 0.1 to 1.0%.
【００１１】Ｓ：被削性改善のために必要な元素であ
り、強度レベルに応じて適宜添加される。しかし、その
量が０．１％を超えるとＭｎＳの量、サイズが増大し、
疲労強度が低下する。従ってＳ量を０．１％以下に規定
する。S: An element necessary for improving machinability, and is appropriately added according to the strength level. However, when the amount exceeds 0.1%, the amount and size of MnS increase,
Fatigue strength decreases. Therefore, the amount of S is regulated to 0.1% or less.
【００１２】Ｃｒ：窒化特性を向上させる元素である
が、０．５％未満ではその効果が得られない。一方、そ
の量が２．０％を超えると靱性が低下する。従ってＣｒ
含有量を０．５〜２．０％の範囲に規定する。[0012] Cr: an element for improving the nitriding properties, but if less than 0.5%, the effect cannot be obtained. On the other hand, if the amount exceeds 2.0%, the toughness decreases. Therefore Cr
The content is specified in the range of 0.5 to 2.0%.
【００１３】Ｍｏ：Ｖと複合添加することにより有効硬
化深さを著しく向上させる機能を有する。しかし、その
量が１．５％未満ではその機能を有効に発揮することが
できず、２．５％を超えると効果が飽和するとともにコ
ストアップにつながる。従ってＭｏ含有量を１．５〜
２．５％の範囲に規定する。It has a function of remarkably improving the effective curing depth by being combined with Mo: V. However, if the amount is less than 1.5%, the function cannot be effectively exhibited, and if it exceeds 2.5%, the effect is saturated and the cost is increased. Therefore, when the Mo content is 1.5 to
It is specified in the range of 2.5%.
【００１４】Ｖ：Ｍｏと複合添加することにより有効硬
化深さを向上させる元素であるが、０．０５％未満では
その効果が得られない。一方、その量が０．２％以上で
は表面硬さが大きくなりすぎる。従ってＶ含有量を０．
０５％以上、０．２％未満に規定する。V: An element which improves the effective hardening depth by adding Mo in combination with Mo. However, if it is less than 0.05%, the effect cannot be obtained. On the other hand, if the amount is 0.2% or more, the surface hardness becomes too large. Therefore, the V content is set to 0.
Defined to be at least 05% and less than 0.2%.
【００１５】Ａｌ：Ａｌは、一定量以上の存在下で窒化
処理を行うことにより、表面硬さを上昇させ、疲労強度
を低下させる作用を有する。従って、Ａｌの含有量をこ
のような作用を及ぼさない０．０５％以下に規定する。
本発明の窒化用鋼は、上述のような組成を有している限
り、その製造方法は問わず、その用途に応じて適宜製造
方法が選択される。Al: Al has an effect of increasing surface hardness and lowering fatigue strength by performing nitriding treatment in the presence of a certain amount or more. Therefore, the content of Al is defined to be 0.05% or less which does not exert such an effect.
As long as the steel for nitridation of the present invention has the above-described composition, its production method is not limited, and a production method is appropriately selected according to its use.
【００１６】また、本発明の窒化用鋼に窒化処理を施す
に際しても、その処理方法は特に限定されず、通常行わ
れている窒化処理方法、例えばガス窒化処理法を適用す
ることができる。The nitriding treatment of the steel for nitriding of the present invention is not particularly limited, and a conventional nitriding treatment, for example, a gas nitriding treatment can be applied.
【００１７】なお、一層大きな有効硬化深さを得る観点
からは、窒化処理開始から窒化処理終了までの間温度を
連続的に上昇させる方法（以後、傾斜窒化法と呼ぶ）
が、温度を一定に保持して窒化処理を行う従来の方法よ
りも好ましい。この傾斜窒化法においては、窒化処理開
始温度を４８０〜５５０℃の範囲内に設定し、窒化処理
終了温度を５６０〜６３０℃の範囲内に設定することに
より良好な結果が得られる。また、連続的に昇温させる
態様は問わないが、直線的に昇温することがより好まし
い。From the viewpoint of obtaining a larger effective hardening depth, a method of continuously increasing the temperature from the start of the nitriding treatment to the end of the nitriding treatment (hereinafter referred to as a gradient nitriding method)
However, it is preferable to the conventional method of performing the nitriding treatment while maintaining the temperature constant. In this gradient nitriding method, good results can be obtained by setting the nitriding treatment start temperature in the range of 480 to 550 ° C and the nitriding treatment end temperature in the range of 560 to 630 ° C. Further, the manner in which the temperature is continuously raised is not limited, but it is more preferable that the temperature be raised linearly.
【００１８】[0018]
【実施例】以下、本発明の実施例について説明する。 （実施例１）表１に示す化学成分の鋼を１５０ｋｇ真空
溶解炉にて溶製後、３０ｍｍφに熱間鍛造し、その後９
５０℃×１時間の焼ならしを行い、供試材とした。Embodiments of the present invention will be described below. (Example 1) 150 kg of steel having the chemical components shown in Table 1 was melted in a vacuum melting furnace, and then hot forged to 30 mmφ, and then 9
Normalization was performed at 50 ° C. × 1 hour to obtain a test material.
【００１９】この供試材を平行部８ｍｍφの小野式回転
曲げ疲労試験片に加工し、この試験片をＮ2 −ＮＨ3 −
ＣＯ2 雰囲気を用いたガス窒化炉にて５８０℃で２０時
間のガス窒化を行った後、疲労試験に供した。試験片の
一部を切断し、この切断片の硬さを測定した。This test material was processed into an Ono-type rotating bending fatigue test piece having a parallel portion of 8 mmφ, and this test piece was N 2 -NH 3-
After performing gas nitriding at 580 ° C. for 20 hours in a gas nitriding furnace using a CO 2 atmosphere, the sample was subjected to a fatigue test. A part of the test piece was cut, and the hardness of the cut piece was measured.
【００２０】表１に表面硬さ、有効硬化深さ、疲労強度
の測定結果を合わせて示す。表１中表面硬さは、表面か
ら０．０５ｍｍ位置の硬さ、有効硬化深さはＨＶ４２０
となる距離、疲労強度は繰返し数１０7 回での応力値で
評価した。なお、番号１〜３は本発明の範囲内の組成で
ある実施例、番号４〜８は本発明の範囲から外れる比較
例である。Table 1 also shows the results of measurement of surface hardness, effective hardening depth, and fatigue strength. In Table 1, surface hardness is hardness at a position of 0.05 mm from the surface, and effective hardening depth is HV420.
Distance and fatigue strength is 10 7 repetitions Evaluation was based on the stress value at each time. In addition, Nos. 1-3 are Examples which are compositions within the scope of the present invention, and Nos. 4-8 are Comparative Examples which are out of the scope of the present invention.
【００２１】[0021]
【表１】 [Table 1]
【００２２】表１から、本発明の範囲内の番号１〜３は
いずれも表面硬さがＨＶ７００〜８００の間にあり、
０．４ｍｍ以上の大きな有効硬化深さが得られ、高い疲
労強度を有することがわかる。From Table 1, numbers 1 to 3 within the scope of the present invention all have a surface hardness between HV 700 to 800,
It can be seen that a large effective hardening depth of 0.4 mm or more is obtained, and that it has high fatigue strength.
【００２３】これに対して、番号４はＣｒが低いため、
番号５はＭｏが低いため、番号６はＶが低いため、いず
れも有効硬化深さが小さく高い疲労強度が得られない。
また、番号７はＡｌが高いため、有効硬化深さは大きい
ものの表面硬さが高過ぎて疲労強度が低下している。番
号８はＳＡＣＭ６４５でＪＩＳの窒化鋼であり、表面硬
さが高く、有効硬化深さが小さいため、高い疲労強度が
得られない。 （実施例２）On the other hand, No. 4 has low Cr,
No. 5 has a low Mo and No. 6 has a low V, so that the effective hardening depth is small and high fatigue strength cannot be obtained.
Further, in No. 7, since Al is high, the effective hardening depth is large, but the surface hardness is too high and the fatigue strength is reduced. No. 8 is SACM645, a JIS nitrided steel, having a high surface hardness and a small effective hardening depth, so that high fatigue strength cannot be obtained. (Example 2)
【００２４】表１に示す本発明の範囲内である番号１の
鋼を実施例１と同様の方法で製造し、疲労試験片に加工
後、以下のＡ〜Ｄに示す窒化パターンでガス窒化処理を
行った。 （Ａ）５８０℃で２０時間保持。 （Ｂ）５００℃から窒化を開始し、連続的に昇温し、６
１０℃で終了。 （Ｃ）５３０℃から窒化を開始し、連続的に昇温し、６
４０℃で終了。 （Ｄ）４７０℃から窒化を開始し、連続的に昇温し、５
８０℃で終了。 そして、これら窒化処理が施された試験片を疲労試験に
供した。なお、Ａ〜Ｄの窒化のパターンを図１に示す。
時間はいずれも２０時間である。表２に表面硬さ、有効
硬化深さ、疲労強度の測定結果を示す。Steel No. 1 within the scope of the present invention shown in Table 1 was produced in the same manner as in Example 1, processed into a fatigue test piece, and then subjected to gas nitriding with the following nitriding patterns A to D. Was done. (A) Hold at 580 ° C. for 20 hours. (B) Nitriding is started from 500 ° C., and the temperature is continuously increased to 6
Finished at 10 ° C. (C) Nitriding is started at 530 ° C., and the temperature is raised continuously,
Finished at 40 ° C. (D) Nitriding was started at 470 ° C., and the temperature was raised continuously to 5
Finish at 80 ° C. Then, the test pieces subjected to the nitriding treatment were subjected to a fatigue test. FIG. 1 shows patterns of nitriding of A to D.
Each time is 20 hours. Table 2 shows the measurement results of surface hardness, effective hardening depth, and fatigue strength.
【００２５】[0025]
【表２】 [Table 2]
【００２６】この表から、窒化処理開始温度を４８０〜
５５０℃、窒化処理終了温度を５６０〜６３０℃に設定
して傾斜窒化法を採用した窒化パターン（Ｂ）で処理す
ることにより、他の窒化パターン（Ａ）、（Ｃ）、
（Ｄ）よりも、疲労強度が高いことが確認された。ま
た、ガス窒化法に代えて、イオン窒化法や塩浴窒化法を
採用した場合においても同様の効果が得られることが確
認された。From this table, it can be seen that the nitriding treatment starting temperature is
By setting the temperature at 550 ° C. and the nitriding treatment end temperature at 560 to 630 ° C. and performing the nitriding pattern (B) employing the gradient nitriding method, other nitriding patterns (A), (C),
It was confirmed that the fatigue strength was higher than (D). It was also confirmed that the same effect was obtained when an ion nitriding method or a salt bath nitriding method was used instead of the gas nitriding method.
【００２７】[0027]
【発明の効果】以上のように、本発明によれば、適度の
表面硬さと０．４ｍｍ以上の大きな有効硬化深さが得ら
れ疲労強度に優れた窒化用鋼を得ることができる。As described above, according to the present invention, it is possible to obtain a nitriding steel having an appropriate surface hardness and a large effective hardening depth of 0.4 mm or more and having excellent fatigue strength.
【図１】窒化処理における温度パターンを示す図。FIG. 1 is a diagram showing a temperature pattern in a nitriding process.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 石黒 守幸 東京都千代田区丸の内一丁目１番２号 日本鋼管株式会社内 (72)発明者 椛澤 均 埼玉県蓮田市大字閏戸2358−１ 株式会 社日本テクノ内 (72)発明者 桑原 美博 新潟県長岡市新保４丁目11−10 (56)参考文献 特開 昭55−145155（ＪＰ，Ａ) 特開 平４−201128（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 - 38/60 ──────────────────────────────────────────────────続 き Continued on the front page (72) Inventor Moriyuki Ishiguro 1-2-1, Marunouchi, Chiyoda-ku, Tokyo Inside Nippon Kokan Co., Ltd. (72) Inventor Yoshihiro Kuwahara 4-11-10, Shinbo, Nagaoka-shi, Niigata (56) References JP-A-55-145155 (JP, A) JP-A-4-201128 (JP, A) (58) ) Field surveyed (Int. Cl. 7 , DB name) C22C 38/00-38/60
Claims (1)
え、０．４５％以下，Ｓｉ：０．０５〜１．０％、Ｍ
ｎ：０．１〜１．０％、Ｓ：０．１０％以下、Ｃｒ：
０．５〜２．０％、Ｍｏ：１．５〜２．５％、Ｖ：０．
０５％以上、０．２％未満、Ａｌ：０．０５％以下を含
有し、残部がＦｅ及び不可避的不純物からなり、窒化処
理による有効硬化深さが０．４ｍｍ以上、表面硬度Ｈｖ
７００〜８００を特徴とする疲労強度に優れた機械構造
部品。 1. The steel component in weight%, C: more than 0.25%, not more than 0.45%, Si: 0.05-1.0%, M
n: 0.1 to 1.0%, S: 0.10% or less, Cr:
0.5-2.0%, Mo: 1.5-2.5%, V: 0.
0.05% to less than 0.2%, Al: 0.05% or less, the balance being Fe and unavoidable impurities, punished nitride
Effective hardening depth of 0.4 mm or more, surface hardness Hv
Machine structure excellent in fatigue strength characterized by 700 to 800
parts.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04938493A JP3283088B2 (en) | 1993-03-10 | 1993-03-10 | Machine structural parts with excellent fatigue strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04938493A JP3283088B2 (en) | 1993-03-10 | 1993-03-10 | Machine structural parts with excellent fatigue strength |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06264177A JPH06264177A (en) | 1994-09-20 |
| JP3283088B2 true JP3283088B2 (en) | 2002-05-20 |
Family
ID=12829530
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP04938493A Expired - Lifetime JP3283088B2 (en) | 1993-03-10 | 1993-03-10 | Machine structural parts with excellent fatigue strength |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3283088B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20110253265A1 (en) | 2010-04-15 | 2011-10-20 | Nisshin Steel Co., Ltd. | Quenched and tempered steel pipe with high fatigue life, and its manufacturing method |
-
1993
- 1993-03-10 JP JP04938493A patent/JP3283088B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH06264177A (en) | 1994-09-20 |
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