JP3318467B2 - Manufacturing method of high strength and high toughness steel pipe with excellent workability - Google Patents
Manufacturing method of high strength and high toughness steel pipe with excellent workabilityInfo
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- JP3318467B2 JP3318467B2 JP15527895A JP15527895A JP3318467B2 JP 3318467 B2 JP3318467 B2 JP 3318467B2 JP 15527895 A JP15527895 A JP 15527895A JP 15527895 A JP15527895 A JP 15527895A JP 3318467 B2 JP3318467 B2 JP 3318467B2
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Description
【０００１】[0001]
【産業上の利用分野】この発明は、鋼管製の自動車構造
部品、特にシリンダーやエアバッグ用鋼管等に代表され
る高寸法精度で加工性に優れ、かつ高強度、高靭性が要
求される圧力容器部品に適した加工性に優れた高強度高
靭性鋼管の製造方法に関する。BACKGROUND OF THE INVENTION The present invention relates to a pressure required to have high dimensional accuracy, excellent workability, high strength and high toughness typified by steel pipe-made automobile structural parts, particularly steel pipes for cylinders and airbags. The present invention relates to a method for producing a high-strength, high-toughness steel pipe having excellent workability suitable for container parts.
【０００２】[0002]
【従来の技術】近年、自動車産業においては、安全性を
追求した装置の導入が積極的に進められており、その中
でも衝突時に乗員がハンドルやインストルメントパネル
などに衝突する前に、それらと乗員の間に不活性ガス等
でエアバッグを展開させて乗員の運動エネルギーを吸収
して障害軽減を図るエアバッグシステムが開発搭載され
るに至っている。エアバッグシステムのエアバッグのア
キュムレータに用いられる鋼管は、高強度、高靭性と共
に、高加工性が要求されている。2. Description of the Related Art In recent years, in the automobile industry, the introduction of safety-related devices has been actively promoted. Among them, an occupant is required to collide with a steering wheel, an instrument panel, or the like before a collision occurs. During this period, an airbag system that deploys an airbag with an inert gas or the like to absorb the kinetic energy of the occupant to reduce obstacles has been developed and installed. BACKGROUND ART A steel pipe used for an accumulator of an airbag of an airbag system is required to have high workability as well as high strength and high toughness.
【０００３】従来、これらの圧力容器の素材としては、
アルミニウムが用いられているが、アルミニウムが高価
なため鋼製への切替えが図られている。鋼製の場合に
は、従来の冷間引抜き加工と焼鈍の組合せでは高強度化
により靭性低下が著しく、上記要求を満足することはで
きない。また、鋼管を焼入れ焼戻しするのみでは、高強
度高靭性高加工性が得られたとしても、所定の高寸法精
度が得られない等の問題点を有していた。Conventionally, the materials for these pressure vessels include:
Although aluminum is used, aluminum is expensive, so switching to steel is being attempted. In the case of steel, in the conventional combination of cold drawing and annealing, the toughness is significantly reduced due to high strength, and the above requirements cannot be satisfied. Further, quenching and tempering of a steel pipe alone has a problem that even if high strength, high toughness and high workability are obtained, a predetermined high dimensional accuracy cannot be obtained.
【０００４】また、他の方法としては、Ｃ：０．１５〜
０．３０％、Ｓｉ：０．０５〜０．５０％、Ｍｎ：０．
３０〜１．００％、Ｐ：０．０４０％以下、Ｓ：０．０
１０％以下を含み、残部がＦｅおよび不可避的不純物か
らなる電縫管を素材とし、焼入れ焼戻しによりベイナイ
ト組織としたのち、冷間抽伸、応力除去焼鈍する方法
（特開平４−１９１３２３号公報）、Ｃ：０．１５〜
０．３０％、Ｓｉ：０．１〜０．７％、Ｍｎ：０．５〜
２．５％、Ｃｒ：０．２〜２．５％、Ｓｏｌ．Ａｌ：
０．０１〜０．０５％を含有し、残部がＦｅおよび不可
避的不純物からなる鋼、またはＣ：０．１５〜０．３０
％、Ｓｉ：０．１〜０．７％、Ｍｎ：０．５〜２．５
％、Ｃｒ：０．２〜２．５％、Ｓｏｌ．Ａｌ：０．０１
〜０．０５％と、Ｍｏ：０．０５〜１．０％、Ｖ：０．
０２〜０．１％、Ｎｉ：０．２〜２．５％、Ｔｉ：０．
０２〜０．１０％、Ｎｂ：０．０２〜０．１０％、Ｂ：
０．０００５〜０．００５％のうちの１種以上を含有
し、残部がＦｅおよび不可避的不純物からなる鋼を素材
として、熱間圧延により熱延鋼板とし、軟化焼鈍後、管
状に成形、溶接して製造された鋼管を、所定の部品形状
となるように冷間加工した後、８５０〜１０５０℃で
０．５〜３０分間間加熱後空冷する方法（特開平５−３
０２１１９号公報）等が提案されている。As another method, C: 0.15 to 0.15
0.30%, Si: 0.05 to 0.50%, Mn: 0.
30 to 1.00%, P: 0.040% or less, S: 0.0
A method in which an electric resistance welded tube containing 10% or less, the balance being Fe and unavoidable impurities is used as a material, and a bainite structure is formed by quenching and tempering, followed by cold drawing and stress relief annealing (Japanese Patent Laid-Open No. 4-191323); C: 0.15
0.30%, Si: 0.1 to 0.7%, Mn: 0.5 to
2.5%, Cr: 0.2-2.5%, Sol. Al:
Steel containing 0.01 to 0.05%, with the balance being Fe and unavoidable impurities, or C: 0.15 to 0.30
%, Si: 0.1 to 0.7%, Mn: 0.5 to 2.5
%, Cr: 0.2 to 2.5%, Sol. Al: 0.01
-0.05%, Mo: 0.05-1.0%, V: 0.
02-0.1%, Ni: 0.2-2.5%, Ti: 0.
02 to 0.10%, Nb: 0.02 to 0.10%, B:
A steel containing at least one of 0.0005 to 0.005%, with the balance being Fe and unavoidable impurities, as a material, hot-rolled into a hot-rolled steel sheet, formed into a tube after softening and annealing, and then welded After cold-working the manufactured steel pipe so as to have a predetermined part shape, the steel pipe is heated at 850 to 1050 ° C. for 0.5 to 30 minutes and then air-cooled (Japanese Patent Laid-Open No. 5-3
No. 02119) has been proposed.
【０００５】[0005]
【発明が解決しようとする課題】上記特開平４−１９１
３２３号公報に開示の方法は、ベイナイト組織化による
切削性の向上を図ったものであるが、焼入れによりベイ
ナイト組織を得るためにはどうしてもＣ量を増加させる
必要があり、Ｃ：０．１５〜０．３０％と高い値とする
必要がある。しかしながら、このようにＣ量を高くし、
かつベイナイト組織とした場合は、一般的に延性、靭性
が乏しく、エアバッグ用のアキュムレータ等のような管
端絞り加工されるような用途には不向きであり、しかも
溶接性等にも問題がある。また、特開平５−３０２１１
９号公報に開示の方法は、上記特開平４−１９１３２３
号公報に開示の方法と同様、Ｃ：０．１５〜０．３０％
と高いため、一般的に延性、靭性が乏しく、エアバッグ
用のアキュムレータ等のような管端絞り加工されるよう
な用途には不向きであり、しかも溶接性等にも問題があ
る。SUMMARY OF THE INVENTION The above-mentioned Japanese Patent Application Laid-Open No. 4-191 is disclosed.
Although the method disclosed in Japanese Patent No. 323 aims to improve the machinability by bainite organization, it is necessary to increase the amount of C in order to obtain a bainite structure by quenching, and C: 0.15 to 0.15. It needs to be as high as 0.30%. However, by increasing the amount of C in this way,
In addition, when it has a bainite structure, it generally has poor ductility and toughness, and is not suitable for applications such as accumulators for airbags where pipe end drawing is performed, and has problems in weldability and the like. . In addition, Japanese Patent Application Laid-Open No. 5-30211
The method disclosed in Japanese Patent Application Laid-open No. 9-191323 is disclosed in
: 0.15 to 0.30% as in the method disclosed in
Therefore, it generally has poor ductility and toughness, and is unsuitable for uses such as an accumulator for an air bag which is used for drawing a pipe end, and has a problem in weldability and the like.
【０００６】この発明の目的は、上記従来技術の欠点を
解消し、高寸法精度で加工性に優れ、かつ高強度、高靭
性が要求される圧力容器部品に適した加工性に優れた高
強度高靭性鋼管の製造方法を提供することにある。SUMMARY OF THE INVENTION An object of the present invention is to solve the above-mentioned disadvantages of the prior art, to provide high dimensional accuracy and excellent workability, and to provide high strength excellent in workability suitable for pressure vessel parts requiring high strength and high toughness. An object of the present invention is to provide a method for manufacturing a high toughness steel pipe.
【０００７】[0007]
【課題を解決するための手段】本発明者らは、上記目的
を達成すべく鋭意試験研究を重ねた。その結果、所定の
成分の鋼を製管後、先ず焼入れ焼戻しを行って靭性を付
与した後、所定の寸法精度を得るため冷間加工を行い、
その後焼鈍を実施することによって高寸法精度で加工性
に優れ、かつ高強度、高靭性鋼管が得られることを究明
し、この発明に到達した。Means for Solving the Problems The present inventors have intensively studied and studied to achieve the above object. As a result, after producing steel of a predetermined component, after first performing quenching and tempering to impart toughness, cold working to obtain a predetermined dimensional accuracy,
Thereafter, it was determined that an annealing process was performed to obtain a steel pipe having high dimensional accuracy, excellent workability, and high strength and high toughness.
【０００８】すなわち本願の第１項の発明は、Ｃ：０．
０５〜０．１５％、Ｓｉ：０．５０％以下、Ｍｎ：０．
５０〜２．００％、Ｐ：０．０２０％以下、Ｓ：０．０
２０％以下を含有し、残部がＦｅおよび不可避的不純物
からなる鋼を製管後、８５０〜１０００℃で焼入れし、
４５０℃以上Ａｃ1変態点未満の温度で焼戻しを行った
のち、所定の寸法に冷間引抜き加工を施した後、４５０
℃以上Ａｃ1変態点未満の温度で焼鈍することを特徴と
する加工性に優れた高強度高靭性鋼管の製造方法であ
る。[0008] That is, the invention of the first aspect of the present invention is the invention of C: 0.
0.5 to 0.15%, Si: 0.50% or less, Mn: 0.
50 to 2.00%, P: 0.020% or less, S: 0.0
After producing a steel containing 20% or less, the balance being Fe and unavoidable impurities, the steel is quenched at 850 to 1000 ° C,
After tempering at a temperature of 450 ° C. or higher and lower than the Ac 1 transformation point, after performing cold drawing to a predetermined size,
A method for producing a high-strength, high-toughness steel pipe excellent in workability, characterized by annealing at a temperature of not lower than C 1 and lower than the Ac 1 transformation point.
【０００９】また、本願の第２項の発明は、Ｃ：０．０
５〜０．１５％、Ｓｉ：０．５０％以下、Ｍｎ：０．５
０〜２．００％、Ｐ：０．０２０％以下、Ｓ：０．０２
０％以下と、Ｍｏ：０．０５〜０．５０％、Ｖ：０．０
２〜０．１０％、Ｎｉ：０．０５〜０．５０％、Ｃｒ：
０．０５〜１．００％、Ｃｕ：０．０５〜０．５０％、
Ｔｉ：０．０２〜０．１０％、Ｎｂ：０．０２〜０．１
０％、Ｂ：０．０００５〜０．００５％のうちの１種以
上を含有し、残部がＦｅおよび不可避的不純物からなる
鋼を製管後、８５０〜１０００℃で焼入れし、４５０℃
以上Ａｃ1変態点未満の温度で焼戻しを行ったのち、所
定の寸法に冷間引抜き加工を施した後、４５０℃以上Ａ
ｃ1変態点未満の温度で焼鈍することを特徴とする加工
性に優れた高強度高靭性鋼管の製造方法である。[0009] The invention of the second aspect of the present invention is the invention, wherein C: 0.0
5 to 0.15%, Si: 0.50% or less, Mn: 0.5
0 to 2.00%, P: 0.020% or less, S: 0.02
0% or less, Mo: 0.05 to 0.50%, V: 0.0
2 to 0.10%, Ni: 0.05 to 0.50%, Cr:
0.05 to 1.00%, Cu: 0.05 to 0.50%,
Ti: 0.02 to 0.10%, Nb: 0.02 to 0.1
0%, B: Steel containing at least one of 0.0005 to 0.005%, the balance being Fe and unavoidable impurities, is quenched at 850 to 1000 ° C., and then 450 ° C.
After tempering at a temperature below the Ac 1 transformation point, cold drawing is performed to predetermined dimensions, and then 450 ° C. or more.
This is a method for producing a high-strength, high-toughness steel pipe excellent in workability, characterized by annealing at a temperature lower than the c 1 transformation point.
【００１０】[0010]
【作用】先ずこの発明で使用する鋼材の化学成分に関す
る限定理由は以下のとおりである。Ｃは鋼の必要な強度
を安価に得るために添加する元素であるが、０．０５％
未満では十分な強度が得られず、また、０．１５％を超
えると延性ならびに溶接性が悪化すると共に、靭性が低
下するため、０．０５〜０．１５％とした。Ｓｉは鋼の
冷間加工性を阻害する元素であり、０．５０％を超える
と加工性が悪化するため、０．５０％以下とした。Ｍｎ
は鋼の強度と靭性を向上させるのに有効な元素である
が、０．５０％未満では十分な強度と靭性が得られず、
また、２．００％を超えると溶接性が悪化するため、
０．５０〜２．００％とした。Ｐは粒界偏析に起因する
靭性低下をもたらすため、０．０２０％以下とした。Ｓ
は鋼中のＭｎと化合してＭｎＳによる介在物を形成し、
延性の悪化ならびに靭性を低下させるため、０．０２０
％以下とした。The reasons for limiting the chemical composition of the steel used in the present invention are as follows. C is an element added to obtain the necessary strength of steel at low cost.
If it is less than 0.15%, sufficient strength cannot be obtained, and if it exceeds 0.15%, ductility and weldability are deteriorated and toughness is reduced. Si is an element that inhibits the cold workability of steel, and if it exceeds 0.50%, the workability deteriorates. Mn
Is an effective element for improving the strength and toughness of steel, but if less than 0.50%, sufficient strength and toughness cannot be obtained,
Further, when the content exceeds 2.00%, the weldability deteriorates.
0.50 to 2.00%. Since P causes a decrease in toughness due to grain boundary segregation, P is set to 0.020% or less. S
Combines with Mn in steel to form inclusions by MnS,
To reduce ductility and toughness, 0.020
% Or less.
【００１１】鋼中の上記化学成分を限定することによっ
て、後述する圧力容器用として十分な強度、靭性と高加
工性を得ることができるが、さらにこれらを向上させた
い場合、上記化学成分にさらにＭｏ、Ｖ、Ｎｉ、Ｃｒ、
Ｃｕ、Ｔｉ、Ｎｂ、Ｂを添加することが有効である。こ
れら添加成分の含有量の限定理由は以下のとおりであ
る。Ｍｏは固溶強化により高強度化すると共に、焼入れ
性を向上する効果があるが、０．０５％未満ではこの効
果が十分でなく、逆に０．５０％を超えると溶接部が硬
化し、靭性が低下するため、０．０５〜０．５０％とし
た。Ｖは析出物を生成し強度を向上させる効果がある
が、０．０２％未満ではこの効果が十分でなく、また、
０．１０％を超えると溶接部の靭性が低下するため、
０．０２〜０．１０％とした。Ｎｉは焼入れ性を改善す
ると共に靭性を向上させるのに有効な元素であるが、
０．０５％未満ではその効果が十分でなく、また、０．
５０％を超えてもその作用があるものの高価なため、
０．０５〜０．５０％とした。Ｃｒは鋼の強度と耐食性
を向上させるのに有効な元素であるが、０．０５％未満
ではその効果が十分でなく、また、１．００％を超える
と加工性ならびに溶接部の靭性を低下させるため、０．
０５〜１．００％とした。Ｃｕは鋼の耐食性を向上させ
るのに有効な元素であるが、０．０５％未満ではその効
果が十分でなく、また、０．５０％を超えると熱間加工
性を悪化させるため、０．０５〜０．５０％とした。Ｔ
ｉとＮｂは共に組織を微細化することにより靭性の向上
に有効であるが、０．０２％未満ではその効果が十分で
なく、また、０．１０％を超えると逆に靭性を低下させ
るため、０．０２〜０．１０％とした。Ｂは焼入れ性を
改善するのに有効な元素であるが、０．０００５％未満
ではその効果が十分でなく、また、０．００５％を超え
ると靭性を低下させるため、０．０００５〜０．００５
％とした。By limiting the above chemical components in steel, it is possible to obtain sufficient strength, toughness and high workability for a pressure vessel described later. Mo, V, Ni, Cr,
It is effective to add Cu, Ti, Nb, and B. The reasons for limiting the contents of these additional components are as follows. Mo has the effect of increasing the strength by solid solution strengthening and improving the hardenability, but if less than 0.05%, this effect is not sufficient, and if it exceeds 0.50%, the weld hardens, Since the toughness is reduced, the content is set to 0.05 to 0.50%. V has the effect of forming precipitates and improving the strength, but if it is less than 0.02%, this effect is not sufficient.
If it exceeds 0.10%, the toughness of the weld decreases,
0.02 to 0.10%. Ni is an element effective for improving hardenability and toughness,
If the content is less than 0.05%, the effect is not sufficient.
Even if it exceeds 50%, it has the effect but it is expensive,
0.05 to 0.50%. Cr is an effective element for improving the strength and corrosion resistance of steel. However, if it is less than 0.05%, its effect is not sufficient, and if it exceeds 1.00%, the workability and the toughness of the welded portion are reduced. 0.
05 to 1.00%. Cu is an element effective for improving the corrosion resistance of steel. However, if it is less than 0.05%, its effect is not sufficient, and if it exceeds 0.50%, hot workability is deteriorated. 05 to 0.50%. T
Both i and Nb are effective in improving the toughness by refining the structure, but if the content is less than 0.02%, the effect is not sufficient, and if it exceeds 0.10%, the toughness is reduced. , 0.02 to 0.10%. B is an element effective for improving the hardenability, but if it is less than 0.0005%, its effect is not sufficient, and if it exceeds 0.005%, the toughness is reduced. 005
%.
【００１２】この発明においては、上記のように化学成
分を調整した鋼材を素材として製管する。製管法として
は、熱間圧延鋼帯を用いて電縫溶接する方法と、ビレッ
トを用いて熱間製管する継目無製管法があるが、いずれ
の方法でもよい。このようにして製管された鋼管は、先
ず靭性を付与するための焼入れ焼戻しを行う。焼入れ時
の温度は、８５０℃未満では均一なオーステナイト粒が
得られず、また、焼入れ性低下する問題があり、１００
０℃を超えると結晶粒が粗大化して靭性が低下するた
め、８５０〜１０００℃とした。焼戻し温度は、強度、
延性、靭性が最良となる温度を選択すれば良いが、Ａｃ
1変態点以上の温度になると、変態が開始され所期の目
標とする強度、靭性が得られないため、４５０〜Ａｃ1
点未満としたが、好ましくは５００〜６５０℃である。In the present invention, a pipe is made from a steel material whose chemical composition has been adjusted as described above. As the pipe making method, there are a method of performing electric resistance welding using a hot-rolled steel strip and a seamless pipe making method of hot forming using a billet, and any method may be used. The steel pipe thus manufactured is first subjected to quenching and tempering to impart toughness. If the temperature at the time of quenching is lower than 850 ° C., uniform austenite grains cannot be obtained, and there is a problem that the quenchability is reduced.
If the temperature exceeds 0 ° C., the crystal grains become coarse and the toughness is reduced. Tempering temperature, strength,
The temperature at which the ductility and toughness are the best may be selected.
As the 1 transformation point or higher temperatures, the strength of the intended target transformation begins, toughness is not obtained, 450～Ac 1
Lower than the temperature, but preferably 500 to 650 ° C.
【００１３】焼入れ焼戻し後の冷間引抜き加工は、所定
の寸法精度が得られる最適条件下で処理すればよく、特
に加工度を規定する必要はない。最終の軟化焼鈍は、目
標の強度と延性、靭性を付与するために重要である。特
にＡｃ1変態点以上の温度で加熱すると変態が開始さ
れ、特に延性、靭性の低下と強度バラツキが発生するた
め、軟化焼鈍温度は４５０〜Ａｃ1点未満としたが、好
ましくは５００〜６５０℃である。[0013] The cold drawing after quenching and tempering may be carried out under the optimum condition for obtaining a predetermined dimensional accuracy, and it is not particularly necessary to define the working degree. The final soft annealing is important for imparting the desired strength, ductility and toughness. In particular, when heating is performed at a temperature equal to or higher than the Ac 1 transformation point, transformation starts, and particularly, ductility, toughness is reduced, and strength variation occurs. Therefore, the softening annealing temperature is set to 450 to less than Ac 1 point, preferably 500 to 650 ° C. It is.
【００１４】[0014]
実施例１ 表１に示す化学成分の本発明鋼および表２に示す化学成
分の比較鋼のビレットを用い、マンネスマン−マンドレ
ルミル方式による穿孔機、マンドレルミル、レデューサ
圧延により外径７０ｍｍ、肉厚３．２ｍｍに仕上げたの
ち、焼入れなし、または８００〜１０５０℃に１５分間
加熱して焼入れしたのち、５００〜７５０℃で３０分間
焼戻しを行った継目無鋼管を、冷間引抜き加工して外径
６０ｍｍ、肉厚２．５ｍｍに仕上げ、さらにその後５５
０〜７５０℃の温度で焼鈍を行ったのち、各種の特性を
評価した。その結果を表３および表４に示す。なお、特
性の評価は、強度、靭性、延性について実施した。強度
については、ＪＩＳ Ｚ２２０１の金属材料引張試験片
に規定の１１号試験片を用い、ＪＩＳＺ２２４１の金属
材料引張試験方法に準じて引張試験を行った。靭性につ
いては、ＪＩＳ Ｚ２２０２の金属材料衝撃試験片に規
定の４号試験片を用いた。なお、試験片を加工するに際
しては、鋼管を板状にへん平加工したのち、長手方向よ
り板厚２．５ｍｍの試験片を採取し、ＪＩＳ Ｚ２２４
２の金属材料衝撃試験方法に準じて衝撃試験を実施し、
−４０℃における吸収エネルギーを求めて評価した。延
性については、へん平性で評価した。なお、へん平性
は、図１に示すとおり、は、先端Ｒが１０ｍｍのＶブロ
ック（６０°）の押工具１、１を用いて鋼管２が密着す
るまでへん平にし、肩部３に割れの発生有無により評価
し、割れの発生無は○、割れの発生有は×とした。Example 1 A billet made of a steel of the present invention having the chemical components shown in Table 1 and a comparative steel having the chemical components shown in Table 2 were subjected to a mannesmann-mandrel mill-type punch, a mandrel mill, and reducer rolling to obtain an outer diameter of 70 mm and a wall thickness of 3 After finishing to 2 mm, without quenching, or after quenching by heating at 800 to 1050 ° C. for 15 minutes, and then tempering at 500 to 750 ° C. for 30 minutes, the seamless steel pipe was cold drawn to an outer diameter of 60 mm. , Finished to a thickness of 2.5 mm, and then 55
After annealing at a temperature of 0 to 750 ° C, various characteristics were evaluated. The results are shown in Tables 3 and 4. The evaluation of the properties was performed for strength, toughness, and ductility. Regarding the strength, a tensile test was performed according to the JIS Z2241 metal material tensile test method using a specified No. 11 test piece as a metal material tensile test piece according to JIS Z2201. Regarding toughness, a specified No. 4 test piece was used as a metal material impact test piece according to JIS Z2202. When processing the test piece, after flattening the steel pipe into a plate shape, a test piece having a plate thickness of 2.5 mm was sampled from the longitudinal direction, and was subjected to JIS Z224.
Conduct an impact test according to the metal material impact test method of 2,
The absorption energy at -40 ° C was determined and evaluated. The ductility was evaluated by flatness. As shown in FIG. 1, the flatness was flattened using pressing tools 1 and 1 of a V-block (60 °) having a tip R of 10 mm until the steel pipe 2 came into close contact, and the shoulder 3 was cracked. Was evaluated according to the presence or absence of cracks.
【００１５】[0015]
【表１】 [Table 1]
【００１６】[0016]
【表２】 [Table 2]
【００１７】[0017]
【表３】 [Table 3]
【００１８】[0018]
【表４】 [Table 4]
【００１９】表１、表３に示すとおり、鋼Ｎｏ．１〜２
３の本発明鋼は、いずれの成分、プロセスにおいても、
引張強さが６０ｋｇｆ／ｍｍ2以上の高強度で、しか
も、シャルピー衝撃試験における吸収エネルギーが２ｋ
ｇｆ−ｍ以上、さらに密着へん平後の肩部の割れがな
く、良好な加工性を有していた。これに対し、表２、表
４に示すとおり、鋼Ｎｏ．２４〜３６の比較鋼は、鋼Ｎ
ｏ．２４、２７、３０、３３が引張強さが６０ｋｇｆ／
ｍｍ2以下で強度不足、鋼Ｎｏ．３４が引張強さが６０
ｋｇｆ／ｍｍ2以下で、しかもシャルピー衝撃試験にお
ける吸収エネルギーが２ｋｇｆ−ｍ以下で強度ならびに
靭性が不足している。また、鋼Ｎｏ．２６、３２は、密
着へん平後の肩部の割れが発生し、加工性が不足してい
る。さらに、鋼Ｎｏ．２５、２８、２９、３１、３５、
３６は、シャルピー衝撃試験における吸収エネルギーが
２ｋｇｆ−ｍ以下で、しかも密着へん平後の肩部の割れ
が発生し、靭性ならびに加工性が不足している。なお、
本実施例では、継目無鋼管の例を示したが、溶接鋼管を
用いても同一の特性が得られることはいうまでもない。As shown in Tables 1 and 3, the steel No. 1-2
3. The steel of the present invention of 3
High tensile strength of 60 kgf / mm 2 or more and absorption energy of 2 k in Charpy impact test
gf-m or more, and further, there was no cracking of the shoulder after flattening, and good workability was obtained. On the other hand, as shown in Tables 2 and 4, steel No. The comparative steels 24 to 36 are steel N
o. 24, 27, 30, and 33 have a tensile strength of 60 kgf /
mm 2 or less, the strength is insufficient. 34 has a tensile strength of 60
kgf / mm 2 or less, and the absorbed energy in a Charpy impact test is 2 kgf-m or less, resulting in insufficient strength and toughness. In addition, steel No. In Nos. 26 and 32, cracking of the shoulder after flattening was caused, and workability was insufficient. Furthermore, steel No. 25, 28, 29, 31, 35,
In No. 36, the absorbed energy in the Charpy impact test was 2 kgf-m or less, and the shoulder was cracked after flattening, and the toughness and workability were insufficient. In addition,
In the present embodiment, an example of a seamless steel pipe has been described, but it goes without saying that the same characteristics can be obtained even when a welded steel pipe is used.
【００２０】[0020]
【発明の効果】以上述べたとおり、この発明方法によれ
ば、自動車構造部品、特にシリンダーやエアバック用の
アキュムレータ等の用途に適した高寸法精度で加工性に
優れ、かつ高強度、高靭性鋼管を得ることができる。As described above, according to the method of the present invention, high dimensional accuracy and excellent workability, and high strength and high toughness suitable for use in automobile structural parts, particularly cylinders and accumulators for airbags, etc. Steel pipe can be obtained.
【図１】実施例における密着へん平試験方法説明のため
の概略説明図である。FIG. 1 is a schematic explanatory view for explaining an adhesion flatness test method in an example.
１ 押工具 ２ 鋼管 ３ 肩部 DESCRIPTION OF SYMBOLS 1 Press tool 2 Steel pipe 3 Shoulder
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｃ２２Ｃ 38/54 Ｃ２２Ｃ 38/54 ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification code FI C22C 38/54 C22C 38/54
Claims (2)
５０％以下、Ｍｎ：０．５０〜２．００％、Ｐ：０．０
２０％以下、Ｓ：０．０２０％以下を含有し、残部がＦ
ｅおよび不可避的不純物からなる鋼を製管後、８５０〜
１０００℃で焼入れし、４５０℃以上Ａｃ1変態点未満
の温度で焼戻しを行ったのち、所定の寸法に冷間引抜き
加工を施した後、４５０℃以上Ａｃ1変態点未満の温度
で焼鈍することを特徴とする加工性に優れた高強度高靭
性鋼管の製造方法。1. C: 0.05-0.15%, Si: 0.
50% or less, Mn: 0.50 to 2.00%, P: 0.0
20% or less, S: 0.020% or less, the balance being F
e and 850 after steel pipes made of unavoidable impurities
After quenching at 1000 ° C., tempering at a temperature of 450 ° C. or more and less than the Ac 1 transformation point, performing cold drawing to predetermined dimensions, and then annealing at a temperature of 450 ° C. or more and less than the Ac 1 transformation point. A method for producing a high-strength, high-toughness steel pipe excellent in workability, characterized by the following.
５０％以下、Ｍｎ：０．５０〜２．００％、Ｐ：０．０
２０％以下、Ｓ：０．０２０％以下と、Ｍｏ：０．０５
〜０．５０％、Ｖ：０．０２〜０．１０％、Ｎｉ：０．
０５〜０．５０％、Ｃｒ：０．０５〜１．００％、Ｃ
ｕ：０．０５〜０．５０％、Ｔｉ：０．０２〜０．１０
％、Ｎｂ：０．０２〜０．１０％、Ｂ：０．０００５〜
０．００５％のうちの１種以上を含有し、残部がＦｅお
よび不可避的不純物からなる鋼を製管後、８５０〜１０
００℃で焼入れし、４５０℃以上Ａｃ1変態点未満の温
度で焼戻しを行ったのち、所定の寸法に冷間引抜き加工
を施した後、４５０℃以上Ａｃ1変態点未満の温度で焼
鈍することを特徴とする加工性に優れた高強度高靭性鋼
管の製造方法。2. C: 0.05-0.15%, Si: 0.
50% or less, Mn: 0.50 to 2.00%, P: 0.0
20% or less, S: 0.020% or less, Mo: 0.05
０．５0.50%, V: 0.02 to 0.10%, Ni: 0.
05-0.50%, Cr: 0.05-1.00%, C
u: 0.05 to 0.50%, Ti: 0.02 to 0.10.
%, Nb: 0.02 to 0.10%, B: 0.0005 to
After producing a steel containing at least one of 0.005% and the balance being Fe and unavoidable impurities, 850 to 10
After quenching at a temperature of 450 ° C. or more and less than the Ac 1 transformation point, quenching is performed at a predetermined size, and then annealing at a temperature of 450 ° C. or more and less than the Ac 1 transformation point. A method for producing a high-strength, high-toughness steel pipe excellent in workability, characterized by the following.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15527895A JP3318467B2 (en) | 1995-05-29 | 1995-05-29 | Manufacturing method of high strength and high toughness steel pipe with excellent workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15527895A JP3318467B2 (en) | 1995-05-29 | 1995-05-29 | Manufacturing method of high strength and high toughness steel pipe with excellent workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08325641A JPH08325641A (en) | 1996-12-10 |
| JP3318467B2 true JP3318467B2 (en) | 2002-08-26 |
Family
ID=15602413
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15527895A Expired - Lifetime JP3318467B2 (en) | 1995-05-29 | 1995-05-29 | Manufacturing method of high strength and high toughness steel pipe with excellent workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3318467B2 (en) |
Families Citing this family (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2002079526A1 (en) | 2001-03-29 | 2002-10-10 | Sumitomo Metal Industries, Ltd. | High strength steel tube for air bag and method for production thereof |
| US20060070687A1 (en) * | 2002-06-26 | 2006-04-06 | Jfe Steel Corporation, A Corporation Of Japan | Method for producing seamless steel pipe for inflator of air bag |
| US7416617B2 (en) | 2002-10-01 | 2008-08-26 | Sumitomo Metal Industries, Ltd. | High strength seamless steel pipe excellent in hydrogen-induced cracking resistance |
| US20050000601A1 (en) | 2003-05-21 | 2005-01-06 | Yuji Arai | Steel pipe for an airbag system and a method for its manufacture |
| CN101048524B (en) * | 2004-10-29 | 2011-04-13 | 住友金属工业株式会社 | Steel pipe for air bag inflator and method for production thereof |
| US7566416B2 (en) | 2004-10-29 | 2009-07-28 | Sumitomo Metal Industries, Ltd. | Steel pipe for an airbag inflator and a process for its manufacture |
| DE102005046459B4 (en) * | 2005-09-21 | 2013-11-28 | MHP Mannesmann Präzisrohr GmbH | Process for the production of cold-finished precision steel tubes |
| KR101008807B1 (en) | 2006-02-09 | 2011-01-14 | 수미도모 메탈 인더스트리즈, 리미티드 | Method for manufacturing bottle member for air bag inflator |
| CA2667534C (en) | 2006-10-27 | 2013-02-05 | Sumitomo Metal Industries, Ltd. | Seamless steel tube for an airbag accumulator and a process for its manufacture |
| EP2548987B1 (en) * | 2010-03-18 | 2018-08-15 | Nippon Steel & Sumitomo Metal Corporation | Seamless steel pipe for steam injection, and method of manufacturing same |
| CN102676780B (en) * | 2012-05-30 | 2013-10-30 | 江苏华程工业制管股份有限公司 | Hardening and tempering technology of alloy-steel tube |
| CN102861785B (en) * | 2012-09-25 | 2015-04-15 | 攀钢集团成都钢钒有限公司 | Nuclear power-used low-temperature seamless steel tube and production method therefore |
| GB2548175B (en) * | 2016-03-09 | 2018-10-03 | Goodwin Plc | A steel, a welding consumable and a cast steel product |
-
1995
- 1995-05-29 JP JP15527895A patent/JP3318467B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH08325641A (en) | 1996-12-10 |
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