JP2001240913A - Method for producing high strength seamless steel pipe having excellent toughness - Google Patents
Method for producing high strength seamless steel pipe having excellent toughnessInfo
- Publication number
- JP2001240913A JP2001240913A JP2000056461A JP2000056461A JP2001240913A JP 2001240913 A JP2001240913 A JP 2001240913A JP 2000056461 A JP2000056461 A JP 2000056461A JP 2000056461 A JP2000056461 A JP 2000056461A JP 2001240913 A JP2001240913 A JP 2001240913A
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- Prior art keywords
- steel pipe
- reheating
- temperature
- rolling
- toughness
- Prior art date
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、強度と靱性に優れ
た継目無鋼管の製造方法に関し、さらに詳しくは、化学
組成を限定した鋼材を素材として製管するに際し、オン
ラインプロセスによる加工熱処理を採用して、仕上圧延
に引き続く再加熱炉の装入前における鋼管温度を調整す
ることによって、高価な合金鋼を添加することなしに、
靱性に優れた高強度継目無鋼管を製造する方法に関する
ものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a seamless steel pipe having excellent strength and toughness. By adjusting the steel pipe temperature before charging the reheating furnace following the finish rolling, without adding expensive alloy steel,
The present invention relates to a method for producing a high-strength seamless steel pipe having excellent toughness.
【０００２】[0002]
【従来技術】継目無鋼管の製造に多用されているマンネ
スマン・マンドレルミル製管法では、高温に加熱された
ビレットを穿孔圧延機（ピアサー）で穿孔した後、マン
ドレルミルで圧延して中空素管とし、再び加熱、昇温し
た後、ストレッチレデューサで所定の寸法の鋼管に仕上
げ、引き続いて再加熱炉に装入して再加熱した後、次い
で焼入れ・焼戻し処理して、その後は製品鋼管として精
整処理される。2. Description of the Related Art In a Mannesmann mandrel mill tube forming method often used in the production of seamless steel pipes, a billet heated to a high temperature is pierced by a piercing mill (piercer) and then rolled by a mandrel mill to form a hollow shell. After heating and raising the temperature again, the steel pipe was finished to a specified size with a stretch reducer, subsequently placed in a reheating furnace and reheated, then quenched and tempered, and then refined as a product steel pipe. Is processed.
【０００３】このように多くの加工設備や熱処理装置を
必要とする継目無鋼管の製造分野では、省エネルギーや
省プロセスの観点から、オンラインでの加工熱処理を適
用した製造プロセスの簡素化が検討されている。特に、
熱間加工された後に素材が保有する熱を有効利用するこ
とに着目して、仕上圧延後に直ちにオーステナイト温度
まで再加熱し、直接焼入するプロセスが導入されてお
り、それによって大幅な省エネルギーと製造プロセスの
効率化が図れ、工業的に大きなコストダウンが得られる
ようになっている。[0003] In the field of manufacturing seamless steel pipes requiring a large number of processing equipment and heat treatment equipment, simplification of a manufacturing process to which online thermomechanical treatment is applied has been studied from the viewpoint of energy saving and process saving. I have. In particular,
Focusing on the effective use of the heat of the material after hot working, a process of reheating directly to the austenite temperature immediately after finish rolling and directly quenching has been introduced, thereby significantly saving energy and manufacturing The efficiency of the process can be improved, and a large cost reduction can be obtained industrially.
【０００４】ところで、仕上圧延後に直接焼入するオン
ラインプロセスを採用するようになると、製造された製
品鋼管の結晶粒径が粗大となり易く、靱性および耐食性
が低下するという問題が生じている。このような問題に
対応するため、従来から、直接焼入するプロセスを採用
する場合であっても、仕上圧延された鋼管の結晶粒を微
細にすることができる、種々の製造方法が提案されてい
る。By the way, if an on-line process of directly quenching after finish rolling is adopted, there is a problem that the crystal grain size of the manufactured product steel pipe tends to be coarse, and the toughness and corrosion resistance are reduced. In order to cope with such a problem, conventionally, various production methods have been proposed that can make the crystal grains of the finish-rolled steel pipe fine even when a direct quenching process is employed. I have.
【０００５】例えば、特開昭63−96215号公報で提案さ
れる製造方法では、結晶粒の微細化を図るため、マンド
レルミル圧延後に素管を350℃以下に急冷して、そのの
ち素管を再び加熱して仕上圧延を実施することとしてい
る。すなわち、仕上圧延の前に、マンドレルミル圧延さ
れた中空素管に急速冷却と再加熱とを組み合わせること
によって、仕上圧延された鋼管の結晶粒を微細にしよう
とする方法である。For example, in the manufacturing method proposed in Japanese Patent Application Laid-Open No. 63-96215, in order to reduce the size of crystal grains, the raw tube is rapidly cooled to 350 ° C. or less after mandrel mill rolling, and then the raw tube is cooled. The finish rolling is performed by heating again. That is, prior to the finish rolling, a method is used in which the crystal grains of the finish-rolled steel pipe are made fine by combining rapid cooling and reheating on the hollow shell that has been mandrel mill-rolled.
【０００６】しかしながら、提案された製造方法を操業
プロセスに適用しようとすると、穿孔圧延、マンドレル
ミル圧延から仕上圧延までの工程が複雑になるととも
に、エネルギー消費が大きく、強制冷却設備等の投資も
必要となる。このため、オンラインプロセスによる加工
熱処理を採用しても、省エネルギーや省プロセスが不充
分となり、大幅な製造コスト削減が望めないという問題
がある。However, if the proposed manufacturing method is applied to an operation process, the steps from piercing rolling, mandrel mill rolling to finish rolling become complicated, energy consumption is large, and investment in forced cooling equipment and the like is required. Becomes For this reason, even if the thermomechanical treatment by the on-line process is adopted, there is a problem that energy saving and process saving become insufficient, and a significant reduction in manufacturing cost cannot be expected.
【０００７】[0007]
【発明が解決しようとする課題】前述の通り、従来のオ
ンラインプロセスによる加工熱処理では、仕上圧延前に
強制冷却と再加熱とを組み合わせて実施することによっ
て、製品鋼管として必要な靱性、耐食性を確保してい
た。このため、エネルギー消費が大きく、強制設備等の
投資も必要となり、継目無鋼管の効率生産の面からは充
分な対策になり得ていない。As described above, in the conventional thermomechanical heat treatment using an on-line process, the toughness and corrosion resistance required for a product steel pipe are secured by performing a combination of forced cooling and reheating before finish rolling. Was. For this reason, energy consumption is large, investment of forced facilities and the like is required, and it cannot be a sufficient measure from the viewpoint of efficient production of seamless steel pipes.
【０００８】本発明は、上記の問題点に鑑みてなされた
ものであり、素材となる鋼材の化学組成を限定し、仕上
圧延に引き続く再加熱炉の装入前での鋼管温度を調整す
ることによって、高価な合金鋼を添加することなしに、
靱性に優れた高強度継目無鋼管の製造方法を提供するこ
とを目的としている。[0008] The present invention has been made in view of the above problems, and it is an object of the present invention to limit the chemical composition of a steel material to be used as a raw material and adjust the temperature of a steel pipe before charging a reheating furnace subsequent to finish rolling. Without adding expensive alloy steel,
An object of the present invention is to provide a method for manufacturing a high-strength seamless steel pipe having excellent toughness.
【０００９】[0009]
【課題を解決するための手段】本発明者は、上述の課題
を解決するため、種々の化学組成の鋼材を対象として、
数多くの研究を重ねた結果、オンライン熱処理を採用し
た製造プロセスであっても、仕上圧延後から再加熱炉装
入までの時間を調整することによって、結晶粒の微細化
が得られ、通常のオフライン熱処理と同様の性能を持っ
た継目無鋼管が製造できることを知見した。また、上記
の時間調整は、仕上圧延後から再加熱炉装入までの搬送
コンベヤーや搬送用トレイの動作速度を変化させる程度
で可能であることを明らかにした。Means for Solving the Problems In order to solve the above-mentioned problems, the present inventors have aimed at steel materials of various chemical compositions.
As a result of extensive research, even in a manufacturing process that employs online heat treatment, finer grains can be obtained by adjusting the time from finish rolling to charging the reheating furnace, and ordinary offline processing can be achieved. It has been found that a seamless steel pipe having the same performance as heat treatment can be manufactured. In addition, it has been clarified that the above-mentioned time adjustment can be performed only by changing the operation speed of the transport conveyor or the transport tray from after the finish rolling until charging into the reheating furnace.
【００１０】本発明は、このような知見に基づいて完成
されたものであり、下記の(1)〜(3)の靱性に優れた高強
度継目無鋼管の製造方法を要旨としている。 (1) 質量％で、Ｃ：0.04〜0.5％、Si：0.1〜1.0％、M
n：0.2〜1.5％、Cr：0.1〜1.5％、Mo：0.01〜1.0％、
Ｐ：0.03％以下、Ｓ：0.003％以下およびAl：0.005〜0.
5％を含有し、残部はFeおよび不可避的不純物からなる
鋼材を素材として、穿孔後仕上圧延を行い、引き続いて
再加熱炉への装入温度をAc1−100℃以下で850〜1000℃
の温度条件で保持して再加熱を行い、その後直ちに焼入
れを行うことを特徴とする靱性に優れた高強度継目無鋼
管の製造方法である。 (2) 上記(1)の鋼材に、さらに質量％で、Ti：０〜0.5
％、Nb：０〜0.1％、Ｂ：０〜0.01％、Ｖ：０〜0.15
％、Cu：０〜1.0％、Ni：０〜1.0％およびCa：０〜0.00
4％を含有するのが望ましい。 (3) 上記(1)、(2)の製造方法では、再加熱炉への装入温
度は、仕上圧延後に測定された鋼管の圧延仕上温度に基
づいて、搬送コンベア速度および／またはトレイ動作速
度を変化させて、圧延後から再加熱炉装入までの時間を
調整するようにするのが望ましい。The present invention has been completed on the basis of such findings, and has a gist of a method for producing a high-strength seamless steel pipe having excellent toughness described in the following (1) to (3). (1) In mass%, C: 0.04 to 0.5%, Si: 0.1 to 1.0%, M
n: 0.2-1.5%, Cr: 0.1-1.5%, Mo: 0.01-1.0%,
P: 0.03% or less, S: 0.003% or less and Al: 0.005-0.
5%, the remainder is made of steel material consisting of Fe and unavoidable impurities, and after finish drilling, finish rolling is performed, and then the charging temperature to the reheating furnace is 850-1000 ° C below Ac 1 -100 ° C.
And performing quenching immediately after holding under the above temperature conditions, and then manufacturing a high-strength seamless steel pipe excellent in toughness. (2) In addition to the steel material of (1) above, Ti: 0 to 0.5
%, Nb: 0 to 0.1%, B: 0 to 0.01%, V: 0 to 0.15
%, Cu: 0 to 1.0%, Ni: 0 to 1.0%, and Ca: 0 to 0.00
It is desirable to contain 4%. (3) In the manufacturing method of the above (1), (2), the charging temperature to the reheating furnace is based on the rolling finish temperature of the steel pipe measured after finish rolling, the conveyor speed and / or tray operating speed. And it is desirable to adjust the time from rolling to charging into the reheating furnace.
【００１１】[0011]
【発明の実施の形態】本発明において、鋼材の化学組成
および製造方法を上記のように限定した理由を説明す
る。まず、鋼材に高強度および高靱性の特性を具備させ
るのに有効な化学組成について説明する。ここで化学組
成％は、質量％を示す。 １．鋼材の化学組成 Ｃ：0.04〜0.5％ Ｃは、鋼材の焼入れ性を高め、強度を向上させるために
必要な元素である。含有量が0.04％未満では、焼入れ性
が不足して高強度が得られない。一方、0.5％を超えて
含有させると、焼き割れ、遅れ破壊が発生し易くなり、
継日無鋼管の安定製造が困難になる。このため、Ｃ含有
量は、0.04〜0.5％とする。BEST MODE FOR CARRYING OUT THE INVENTION In the present invention, the reasons for limiting the chemical composition of a steel material and the production method as described above will be described. First, a chemical composition effective for providing a steel material with high strength and high toughness characteristics will be described. Here, the chemical composition% indicates mass%. 1. Chemical composition of steel C: 0.04 to 0.5% C is an element necessary for improving the hardenability of the steel and improving the strength. If the content is less than 0.04%, hardenability is insufficient and high strength cannot be obtained. On the other hand, if the content exceeds 0.5%, quenching cracking and delayed fracture tend to occur,
It becomes difficult to manufacture steel pipes continuously for a long time. For this reason, the C content is set to 0.04 to 0.5%.
【００１２】Si：0.1〜1.0％ Siは、鋼の脱酸元素として有効な元素であると同時に、
鋼材の強度を向上する作用がある。脱酸元素としての効
果を発揮するには、0.1％以上の含有が必要であが、1.0
％を超えて含有した場合には、靱性の劣化が見られる。
このため、Si含有量は、0.1〜1.0％とする。Si: 0.1-1.0% Si is an effective element as a deoxidizing element for steel,
It has the effect of improving the strength of steel. In order to exhibit the effect as a deoxidizing element, the content of 0.1% or more is necessary.
%, The toughness is deteriorated.
Therefore, the Si content is set to 0.1 to 1.0%.
【００１３】Mn：0.2〜1.5％ Mnは、鋼の脱酸、脱硫作用を発揮するが、この作用を発
揮させるためには0.2％以上の含有が必要である。一
方、含有量が1.5％を超えると靱性の劣化が見られる。
このため、Mn含有量は、0.2〜1.5％とする。Mn: 0.2 to 1.5% Mn exerts a deoxidizing and desulfurizing action on steel, but it is necessary to contain 0.2% or more in order to exert this action. On the other hand, if the content exceeds 1.5%, toughness is deteriorated.
For this reason, the Mn content is set to 0.2 to 1.5%.
【００１４】Cr：0.1〜1.5％ Crは、焼入れ性を向上させると同時に、強度を増加させ
るので有効な元素である。しかし、その含有量が0.1％
未満ではこれらの効果が得られず、また、1.5％を超え
ると靱性が劣化する。このため、Cr含有量は、0.1〜1.5
％とする。Cr: 0.1-1.5% Cr is an effective element because it improves the hardenability and at the same time increases the strength. However, its content is 0.1%
If it is less than 1.5%, these effects cannot be obtained, and if it exceeds 1.5%, toughness deteriorates. Therefore, the Cr content is 0.1 to 1.5
%.
【００１５】Mo：0.01〜1.0％ Moは、鋼材の焼入れ性を向上させるとともに、焼戻し軟
化抵抗を高める作用を発揮する。これらの作用を発揮さ
せるためには、0.01％以上の含有が必要であり、一方、
1.0％を超えて含有させると、靱性が劣化する。そのた
め、Mo含有量は、0.01〜1.0％とする。Mo: 0.01 to 1.0% Mo improves the hardenability of the steel material and exerts the effect of increasing the tempering softening resistance. In order to exert these effects, the content of 0.01% or more is necessary.
If the content exceeds 1.0%, the toughness deteriorates. Therefore, the Mo content is set to 0.01 to 1.0%.
【００１６】Ｐ：0.03％以下 Ｐは、不純物として鋼中に不可避的に存在する。含有量
が0.03％を超えると、粒界に偏析して靱性を低下させる
ので、その含有は0.03％以下とする。P: 0.03% or less P is inevitably present in steel as an impurity. If the content exceeds 0.03%, segregation at the grain boundaries lowers the toughness, so the content is made 0.03% or less.
【００１７】Ｓ：0.003％以下 Ｓは、不純物として鋼中に不可避的に存在する。過剰に
含有すると、鋼中に介在物として存在して靱性を劣化さ
せるため、その含有は0.003％以下とする。S: 0.003% or less S is inevitably present in steel as an impurity. If it is contained excessively, it is present as inclusions in the steel and deteriorates toughness, so the content is made 0.003% or less.
【００１８】Al：0.005〜0.5％ Alは、鋼の脱酸材として有用な元素であるが、0.005％
未満の含有ではその効果が得られず、一方、0.5％を超
えて含有させると、介在物が多くなって靱性が低下す
る。このため、Al含有量は0.005〜0.5％とする。Al: 0.005 to 0.5% Al is an element useful as a deoxidizing material for steel.
If the content is less than 0.5%, the effect cannot be obtained. On the other hand, if the content exceeds 0.5%, the inclusions increase and the toughness is reduced. For this reason, the Al content is set to 0.005 to 0.5%.
【００１９】Ti：０〜0.5％ Tiは、添加しなくてもよい。添加すると、鋼材の焼入れ
性の確保に有効であり、さらに圧延された鋼管の細粒化
に効果を発揮する。しかし、含有量が0.5％を超える
と、靱性を低下させる。したがって、Tiを添加する場合
には、その含有量は0.5％以下とする。Ti: 0 to 0.5% Ti need not be added. When added, it is effective in ensuring the hardenability of the steel material, and is also effective in reducing the grain size of the rolled steel pipe. However, if the content exceeds 0.5%, the toughness decreases. Therefore, when Ti is added, its content is set to 0.5% or less.
【００２０】Nb：０〜0.1％ Nbは、添加しなくてもよい。添加すると、鋼材の焼入れ
性の確保に有効であり、さらに圧延された鋼管の細粒化
に有効である。しかし、含有量が0.1％を超えると、靱
性を低下させる。したがって、Nbを添加する場合には、
その含有量は0.1％以下とする。Nb: 0 to 0.1% Nb may not be added. When added, it is effective in ensuring the hardenability of the steel material, and is also effective in refining the rolled steel pipe. However, if the content exceeds 0.1%, the toughness decreases. Therefore, when adding Nb,
Its content should be 0.1% or less.
【００２１】Ｂ：０〜0.01％ Ｂは、添加しなくてもよい。添加すると、微量の含有で
あっても焼入れ性を向上させるので、より高強度が必要
な場合に添加すると有効である。しかし、過剰の含有
は、靱性を低下し、焼き割れ感受性を強くする。したが
って、Ｂを添加する場合には、その含有量は0.01％以下
とする。B: 0 to 0.01% B may not be added. The addition improves the hardenability even if contained in a trace amount, so it is effective to add it when higher strength is required. However, an excessive content lowers toughness and increases quenching crack susceptibility. Therefore, when B is added, its content is set to 0.01% or less.
【００２２】Ｖ：０〜0.15％ Ｖは、添加しなくてもよい。添加すると、焼戻し軟化抵
抗および焼入れ性を向上させる。しかし、0.15％を超え
て含有させると、靱性を著しく低下させる。したがっ
て、Ｖを添加する場合には、その含有量は0.15％以下と
する。V: 0 to 0.15% V may not be added. When added, temper softening resistance and hardenability are improved. However, when the content exceeds 0.15%, the toughness is significantly reduced. Therefore, when V is added, its content is set to 0.15% or less.
【００２３】Cu：０〜1.0％ Cuは、添加しなくてもよい。添加すると、鋼材の強度上
昇および耐食性向上に有効である。そのため、必要に応
じて添加されるが、1.0％以上超えて含有しても、コス
ト上昇に見合った性能の改善が見られない。したがっ
て、Cuを添加する場合には、その含有量は1.0％以下と
する。Cu: 0 to 1.0% Cu need not be added. When added, it is effective for increasing the strength of the steel material and improving the corrosion resistance. Therefore, although it is added as needed, even if it exceeds 1.0%, the improvement of the performance corresponding to the cost increase is not seen. Therefore, when adding Cu, the content is set to 1.0% or less.
【００２４】Ni：０〜1.0％ Niは、添加しなくてもよい。添加すると、鋼材の強度上
昇および耐食性向上に有効である。しかし、1.0％以上
超えて含有しても、コスト上昇に見合った性能の改善が
見られない。したがって、Niを添加する場合には、その
含有量は1.0％以下とする。Ni: 0 to 1.0% Ni need not be added. When added, it is effective for increasing the strength of the steel material and improving the corrosion resistance. However, even if the content exceeds 1.0%, the performance is not improved in proportion to the cost increase. Therefore, when adding Ni, the content is set to 1.0% or less.
【００２５】Ca：０〜0.004％ Caは、添加しなくてもよい。Caは添加すると、脱硫効果
が大きくなり、水素誘起割れ等の抑制に有効である。し
かし、含有量が0.004％を超えると、Ca系介在物の生成
を促し、清浄度の低下によって靱性を劣化させる。その
ため、Caを添加する場合には、その含有量は0.004％以
下とする。 ２．製造方法 本発明の製造方法では、上記の化学組成を含有する鋼材
を素材として、穿孔圧延を経て仕上圧延を行い、引き続
いて再加熱炉への装入温度をAc1−100℃以下になるよう
に調整し、850〜1000℃の温度条件で保持して再加熱を
行い、その後直ちに焼入れを行うことを特徴としてい
る。以下に、製造方法を上記のように限定した理由を説
明する。Ca: 0 to 0.004% Ca may not be added. When Ca is added, the desulfurization effect increases, which is effective for suppressing hydrogen-induced cracking and the like. However, when the content exceeds 0.004%, the generation of Ca-based inclusions is promoted, and the toughness is deteriorated due to a decrease in cleanliness. Therefore, when adding Ca, the content is set to 0.004% or less. 2. Production method In the production method of the present invention, a steel material containing the above chemical composition is used as a raw material, finish rolling is performed through piercing rolling, and then the charging temperature to the reheating furnace is adjusted to Ac 1 -100 ° C. or lower. The temperature is maintained at 850 to 1000 ° C., reheating is performed, and quenching is performed immediately thereafter. Hereinafter, the reason why the manufacturing method is limited as described above will be described.
【００２６】まず、仕上圧延に引き続く再加熱炉での装
入温度をAc1−100℃以下にするのは、仕上圧延終了時に
オーステナイト相にあった鋼管を、空冷でAc1−100℃以
下まで冷却すると、冷却速度が遅いためフェライト相を
析出する。この後、Ac1−100℃以下の温度から再加熱炉
内でAc3点以上の温度に鋼管を加熱すると、フェライト
からオーステナイトヘの逆変態が起こり、鋼管の結晶粒
を微細にすることができるからである。このとき、再加
熱炉での昇温時の時間短縮、および省エネルギ−の観点
から、再加熱炉での装入温度はAc1−100℃直下にするの
が望ましい。First, the charging temperature in the reheating furnace following the finish rolling is set to Ac 1 -100 ° C. or less because the steel pipe which was in the austenitic phase at the end of the finish rolling is cooled to Ac 1 -100 ° C. or less by air cooling. Upon cooling, a ferrite phase is precipitated due to a slow cooling rate. Thereafter, when the steel pipe is heated from a temperature of Ac 1 −100 ° C. or less to a temperature of Ac 3 or more in a reheating furnace, a reverse transformation from ferrite to austenite occurs, and the crystal grains of the steel pipe can be made fine. Because. At this time, the charging temperature in the reheating furnace is desirably set to just below Ac 1 -100 ° C. from the viewpoints of shortening the time for raising the temperature in the reheating furnace and saving energy.
【００２７】具体的に、オンラインプロセスによる加工
熱処理において、再加熱炉での装入温度がAc1−100℃以
下になるように、圧延後から再加熱炉装入までの時間を
調整するには、次の手順に従うのが望ましい。すなわ
ち、穿孔圧延後、マンドレルミル圧延を経て仕上圧延に
よって鋼管を製管後、圧延仕上温度を測定し、その測定
結果をフィードバックして、搬送コンベア速度、および
／またはトレイ動作速度を変化させて、仕上圧延された
鋼管が圧延終了〜再加熱炉装入まで搬送される時間を調
整する。これにより、再加熱炉への装入温度がAc1−100
℃以下になるように調整できる。Specifically, in the thermomechanical treatment by the online process, the time from the rolling to the charging of the reheating furnace is adjusted so that the charging temperature in the reheating furnace is Ac 1 -100 ° C. or less. It is desirable to follow the following procedure. That is, after piercing and rolling, after producing a steel pipe by finish rolling through mandrel mill rolling, measure the rolling finish temperature, feed back the measurement result, change the conveyor speed, and / or change the tray operating speed, The time required for the finish-rolled steel pipe to be transported from the end of rolling to charging of the reheating furnace is adjusted. As a result, the charging temperature to the reheating furnace was Ac 1 −100
It can be adjusted to be below ° C.
【００２８】通常、仕上圧延装置および再加熱炉の設備
配置にもよるが、仕上圧延された鋼管の寸法、材質およ
び仕上温度の条件から、標準搬送コンベア速度およびト
レイ動作速度による再加熱炉での装入温度を予測する。
この予測結果に基づいて、搬送コンベア速度等を調整
し、鋼管の装入温度が規定条件を満足するようにする。Normally, although it depends on the arrangement of the finish rolling apparatus and the reheating furnace, the dimensions of the finished rolled steel pipe, the material and the finishing temperature, the conditions of the standard heating conveyor speed and tray operating speed in the reheating furnace. Predict the charging temperature.
The conveyor speed and the like are adjusted based on the prediction result so that the charging temperature of the steel pipe satisfies the specified condition.
【００２９】次に、再加熱を850〜1000℃の温度で保持
するのは、再加熱炉の装入温度をAc1−100℃以下に規定
しているため、焼入れ開始温度を確保するために、850
℃以上の再加熱が必要であり、一方、1000℃を超えて再
加熱を行うと、結晶粒の成長が著しくなり、焼入れ後に
おいて靱性が確保できない恐れがあるからである。ま
た、再加熱を上記の温度条件で保持することによって、
再加熱炉内での鋼管毎の均熱性のみならず、長さ方向の
均熱性も保てて、製品鋼管の強度および靱性の性能バラ
ツキを抑制できる。Next, the reason why the reheating is maintained at a temperature of 850 to 1000 ° C. is that the charging temperature of the reheating furnace is regulated to Ac 1 −100 ° C. or less, so that the quenching start temperature is secured. , 850
This is because reheating at a temperature of not less than 1000C is required, and when reheating is performed at a temperature exceeding 1000C, the growth of crystal grains becomes remarkable, and the toughness may not be secured after quenching. Also, by maintaining the reheating under the above temperature conditions,
The uniformity in the length direction as well as the uniformity of each steel pipe in the reheating furnace can be maintained, and the variation in the strength and toughness of the product steel pipe can be suppressed.
【００３０】さらに、圧延時の加工歪みによる再結晶効
果も期待できる。すなわち、再加熱を850〜1000℃の温
度条件で保持することによって、圧延時の加工歪みによ
る再結晶が起こるので、再結晶が誘起され、更なる結晶
粒の微細化が可能となる。これにより、一層優れた靱
性、耐食性の特性が期待できる。Further, a recrystallization effect due to processing strain during rolling can be expected. In other words, by maintaining the reheating at a temperature of 850 to 1000 ° C., recrystallization occurs due to processing strain during rolling, so that recrystallization is induced and further refinement of crystal grains becomes possible. Thereby, more excellent toughness and corrosion resistance can be expected.
【００３１】再加熱炉から抽出後、オーステナイト域か
ら直ちに焼入れを実施することによって、高強度と高靱
性を具備する鋼管を得ることができる。通常、焼入れ後
には、焼戻し処理が行われ、製品鋼管の品質の安定が図
られる。After extraction from the reheating furnace, the steel pipe having high strength and high toughness can be obtained by immediately quenching from the austenite region. Usually, after the quenching, a tempering treatment is performed to stabilize the quality of the product steel pipe.
【００３２】[0032]
【実施例】本発明の継目無鋼管の製造方法の効果を確認
するため、表１に示す化学組成からなる10種の素材鋼を
準備した。EXAMPLES In order to confirm the effects of the method for producing a seamless steel pipe of the present invention, ten kinds of raw steels having the chemical compositions shown in Table 1 were prepared.
【００３３】[0033]
【表１】 準備した素材鋼を加熱炉に装入して、1250℃で２時間以
上保持したのち、ピアサーを用いて穿孔圧延した後、マ
ンドレルミル圧延を経て中空素管として、次いでストレ
ッチレデュサーを用いて仕上圧延を行い、所定の仕上寸
法の鋼管を製管した。その後、圧延仕上温度を測定し、
測定結果に基づいてストレッチレデュサーの出側から再
加熱炉の入側の間に設けられた搬送コンベヤー速度を調
整して、再加熱炉への装入温度を475℃〜869℃と変動さ
せた。その結果を表２に示す。[Table 1] The prepared material steel was charged into a heating furnace, and held at 1250 ° C. for 2 hours or more. After piercing and rolling using a piercer, a hollow shell was passed through mandrel mill rolling, and then using a stretch reducer. Finish rolling was performed to produce a steel pipe having a predetermined finish size. Then, measure the rolling finish temperature,
Based on the measurement results, adjust the speed of the conveyor provided between the exit side of the stretch reducer and the entrance side of the reheating furnace, and change the charging temperature to the reheating furnace from 475 ° C to 869 ° C. Was. Table 2 shows the results.
【００３４】次に、表２に示す保持条件で再加熱した
後、直接焼入れを施して、540℃〜580℃の条件で焼戻し
を実施して、製品鋼管を製造した。さらに従来のオフラ
インプロセスによる焼入れ・焼戻し処理と比較するた
め、従来例として、オフラインで920℃焼入れＱおよび5
40℃〜580℃焼戻しＴを実施した。Next, after reheating under the holding conditions shown in Table 2, it was directly quenched and tempered at 540 ° C. to 580 ° C. to produce a product steel pipe. Furthermore, in order to compare with the quenching and tempering treatment by the conventional off-line process, as a conventional example, quenching at 920 ° C.
40 ° C to 580 ° C tempering T was performed.
【００３５】焼入れままの鋼管からサンプルを採取し、
旧オーステナイト結晶粒度を測定した。また焼戻し後の
鋼管から試験片を切り出し、引張試験（ＹＳ、ＴＳ）お
よびシャルピー試験を行った。その結果を表２に示す。A sample was taken from the as-quenched steel pipe,
The prior austenite grain size was measured. Further, a test piece was cut out from the tempered steel pipe, and a tensile test (YS, TS) and a Charpy test were performed. Table 2 shows the results.
【００３６】[0036]
【表２】 通常、油井管、ラインパイプ等に用いられる鋼管に要求
される強度は、ＹＳで740Mpa以上であり、靱性はvTrsで
-80℃以下であるとされる。したがって、表２の結果か
ら明らかなように、本発明例１〜９では、いずれも本発
明で規定する化学組成および製造条件を満足しているの
で、ASTM規格 E112 で測定のオーステナイト結晶粒は7.
5以上と微細であり、さらに、高強度（ＹＳ≧740Mpa）
および高靱性（vTrs≦-80℃）の特性も具備している。
しかも、これらの性能は、オフライン焼入れ焼戻し処理
した鋼（従来例20、21）と同等のものとなっている。[Table 2] Usually, the strength required for steel pipes used for oil country tubular goods, line pipes, etc. is 740 MPa or more in YS, and the toughness is vTrs.
It is assumed to be below -80 ° C. Therefore, as is clear from the results in Table 2, in each of Examples 1 to 9 of the present invention, the chemical composition and the production conditions specified in the present invention were satisfied, and the austenite crystal grains measured by ASTM standard E112 were 7%. .
5 or more fine and high strength (YS ≧ 740Mpa)
And high toughness (vTrs ≦ −80 ° C.).
Moreover, these performances are equivalent to those of the steel subjected to the off-line quenching and tempering treatment (conventional examples 20, 21).
【００３７】これに対し、比較例10〜12では、再加熱炉
への装入温度、再加熱の保持温度のいずれかまたは両方
が本発明で規定する範囲から外れることによって、特
に、靱性の劣化が著しい。また、比較例13〜19では、本
発明で規定する化学組成を具備しておらず、一部におい
てさらに再加熱条件も満足していないことから（比較例
13〜15）、いずれも靱性の劣化が著しくなっている。On the other hand, in Comparative Examples 10 to 12, when one or both of the charging temperature into the reheating furnace and the reheating holding temperature were out of the ranges specified in the present invention, the toughness was particularly deteriorated. Is remarkable. Further, Comparative Examples 13 to 19 did not have the chemical composition specified in the present invention, and some of them did not satisfy the reheating conditions (Comparative Example
13 to 15), in all cases, the toughness is significantly deteriorated.
【００３８】[0038]
【発明の効果】本発明の継目無鋼管の製造方法によれ
ば、仕上圧延後の再加熱から焼入れまでを連続したオン
ライン加工熱処理する場合であっても、再加熱炉の装入
温度を管理することのよって、高価な合金鋼を添加する
ことなしに、靱性に優れた高強度継目無鋼管を製造する
ことができる。しかも、継目無鋼管の製造に際して、大
幅な省エネルギーとプロセスの効率化が図れ、工業的に
大きなコストダウンが可能になる。According to the method for manufacturing a seamless steel pipe of the present invention, the charging temperature of the reheating furnace is controlled even in the case where continuous online processing and heat treatment from reheating after finish rolling to quenching is performed. Therefore, a high-strength seamless steel pipe having excellent toughness can be manufactured without adding expensive alloy steel. In addition, in the production of seamless steel pipes, significant energy savings and process efficiency can be achieved, and industrially significant cost reductions are possible.
Claims (3)
0％、Mn：0.2〜1.5％、Cr：0.1〜1.5％、Mo：0.01〜1.0
％、Ｐ：0.03％以下、Ｓ：0.003％以下およびAl：0.005
〜0.5％を含有し、残部はFeおよび不可避的不純物から
なる鋼材を素材として、穿孔後仕上圧延を行い、引き続
いて再加熱炉への装入温度をAc1−100℃以下で850〜100
0℃の温度条件で保持して再加熱を行い、その後直ちに
焼入れを行うことを特徴とする靱性に優れた高強度継目
無鋼管の製造方法。(1) In mass%, C: 0.04 to 0.5%, Si: 0.1 to 1.
0%, Mn: 0.2-1.5%, Cr: 0.1-1.5%, Mo: 0.01-1.0
%, P: 0.03% or less, S: 0.003% or less, and Al: 0.005%
0.50.5%, the balance being a steel material consisting of Fe and unavoidable impurities, and performing finish rolling after piercing, and subsequently setting the charging temperature to the reheating furnace to 850 to 100 at Ac 1 -100 ° C. or lower.
A method for producing a high-strength seamless steel pipe excellent in toughness, characterized in that reheating is carried out while maintaining the temperature at 0 ° C., followed by quenching immediately thereafter.
０〜0.5％、Nb：０〜0.1％、Ｂ：０〜0.01％、Ｖ：０〜
0.15％、Cu：０〜1.0％、Ni：０〜1.0％およびCa：０〜
0.004％を含有することを特徴とする靱性に優れた高強
度継目無鋼管の製造方法。2. The steel material according to claim 1, further comprising:
0 to 0.5%, Nb: 0 to 0.1%, B: 0 to 0.01%, V: 0
0.15%, Cu: 0-1.0%, Ni: 0-1.0% and Ca: 0
A method for producing a high-strength seamless steel pipe excellent in toughness characterized by containing 0.004%.
定された鋼管の圧延仕上温度に基づいて、搬送コンベア
速度および／またはトレイ動作速度を変化させて、仕上
圧延後から再加熱炉装入までの時間を調整することを特
徴とする請求項１または請求項２記載の靱性に優れた高
強度継目無鋼管の製造方法。3. The charging temperature to the reheating furnace is determined by changing the conveying conveyor speed and / or the tray operation speed based on the rolling finish temperature of the steel pipe measured after finish rolling, and reheating after finishing rolling. The method for producing a high-strength seamless steel pipe having excellent toughness according to claim 1 or 2, wherein a time until charging into the furnace is adjusted.
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|---|---|---|---|
| JP2000056461A JP4123672B2 (en) | 2000-03-01 | 2000-03-01 | Manufacturing method of high strength seamless steel pipe with excellent toughness |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000056461A JP4123672B2 (en) | 2000-03-01 | 2000-03-01 | Manufacturing method of high strength seamless steel pipe with excellent toughness |
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| Publication Number | Publication Date |
|---|---|
| JP2001240913A true JP2001240913A (en) | 2001-09-04 |
| JP4123672B2 JP4123672B2 (en) | 2008-07-23 |
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ID=18577403
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|---|---|---|---|
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| CN110484814A (en) * | 2019-08-05 | 2019-11-22 | 中国科学院金属研究所 | A kind of high strength steel seamless pipe and preparation method thereof of aerospace containing rare earth |
| WO2023074658A1 (en) | 2021-10-26 | 2023-05-04 | 日本製鉄株式会社 | Steel pipe welding joint |
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