JP2002035805A - Method for manufacturing thin steel plate excellent in surface properties - Google Patents
Method for manufacturing thin steel plate excellent in surface propertiesInfo
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- JP2002035805A JP2002035805A JP2000224324A JP2000224324A JP2002035805A JP 2002035805 A JP2002035805 A JP 2002035805A JP 2000224324 A JP2000224324 A JP 2000224324A JP 2000224324 A JP2000224324 A JP 2000224324A JP 2002035805 A JP2002035805 A JP 2002035805A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、熱間圧延時の割れ
による表面欠陥の少ない薄鋼板の製造方法に関し、特に
連続鋳造後、鋳片を冷却し、再加熱後、または直接、熱
間圧延を行う直送圧延プロセスにおいても、熱間圧延時
に表面における割れの発生が少ない薄鋼板の製造方法に
関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a thin steel sheet having less surface defects due to cracks during hot rolling, and particularly to hot rolling after continuous casting, cooling a slab and reheating, or directly. The present invention also relates to a method for producing a thin steel sheet with less occurrence of cracks on the surface during hot rolling even in a direct rolling process for performing a hot rolling.
【０００２】[0002]
【従来の技術】連続鋳造から熱間圧延まで直接行う直送
圧延プロセスにより、薄鋼板を製造する場合、熱間圧延
での割れに起因した表面欠陥の発生が問題となることが
多い。この種の割れはＣを０．２％以下含有する炭素鋼
において発生する。2. Description of the Related Art When a thin steel sheet is manufactured by a direct-feed rolling process that directly performs from continuous casting to hot rolling, the occurrence of surface defects due to cracks in hot rolling often becomes a problem. This type of cracking occurs in carbon steel containing 0.2% or less of C.
【０００３】熱間圧延での割れの発生原因は、連続鋳造
時のスラブに曲げ変形が加わる際の引張応力により発生
したスラブ表面またはスラブ表層下の割れが、粗圧延で
伸展したものと考えられている。It is considered that the cause of cracks in hot rolling is that cracks on the slab surface or under the slab surface caused by tensile stress when bending deformation is applied to the slab during continuous casting have been extended by rough rolling. ing.
【０００４】特に、直送圧延プロセスにおいては、スラ
ブ手入が不可能であり、スラブに発生した割れはそのま
ま熱延鋼帯や冷延鋼帯などの製品に残存し、製品歩留ま
りを著しく低下させていた。In particular, in the direct rolling process, slab maintenance is not possible, and cracks generated in the slab remain in products such as hot-rolled steel strips and cold-rolled steel strips as they are, which significantly lowers the product yield. Was.
【０００５】このような問題に対し、特公平７−７６３
７５号公報は、凝固後の冷却過程である１２００〜１０
５０℃の温度領域においてスラブを特定時間保持した
後、Ａｒ3点以上で圧延を開始し、鋼片の表面割れを防
止する熱間圧延法を開示している。[0005] To deal with such a problem, Japanese Patent Publication No.
No. 75 discloses a cooling process after solidification of 1200 to 10
A hot rolling method is disclosed in which after a slab is held in a temperature region of 50 ° C. for a specific time, rolling is started at an Ar3 point or higher to prevent surface cracks of a billet.
【０００６】[0006]
【発明が解決しようとする課題】しかし、実機におい
て、本技術を適用した場合、表面欠陥の発生を十分に抑
制することが出来ず、直送圧延プロセスでは、熱間圧延
の温度条件によって割れが発生し、鋳造後、スラブを冷
却後再加熱する方法では、その再加熱条件によって表面
欠陥が発生していた。尚、熱間圧延での割れは一般に赤
熱脆性に起因するとされている。However, when the present technology is applied to an actual machine, the occurrence of surface defects cannot be sufficiently suppressed, and cracks occur in the direct rolling process due to the temperature conditions of hot rolling. However, in the method in which the slab is cooled and then reheated after casting, surface defects are generated depending on the reheating conditions. Incidentally, cracks in hot rolling are generally attributed to red hot embrittlement.
【０００７】そこで、本発明では、連続鋳造から、熱間
圧延まで直接行う直送圧延プロセス及び連続鋳造機、鋳
片を冷却し、再加熱後に粗圧延を行うプロセスを対象
に、熱間圧延での割れに起因した表面欠陥の発生が極め
て少ない表面性状に優れた薄鋼板、特にＴＳ２７０ＭＰ
ａ級以上の薄鋼板の製造方法を提供することを目的とす
る。In view of the above, the present invention is directed to a direct-rolling rolling process in which continuous casting is performed directly from hot rolling to a continuous casting machine, and a process in which a slab is cooled and re-heated to perform rough rolling. Thin steel sheet excellent in surface properties with extremely few surface defects caused by cracks, especially TS270MP
An object of the present invention is to provide a method for producing a steel sheet of class a or higher.
【０００８】[0008]
【課題を解決するための手段】本発明者等は、上記課題
を解決すべく、鋼材の成分組成および連続鋳造機による
鋳造後、熱間圧延までの諸条件について検討し、特定の
成分組成の鋼を鋳造後、一定時間保持し、その後、曲げ
変形を表面温度、表面での歪速度を制御しつつ行ない、
粗圧延における圧延条件を規定した場合、熱間圧延での
割れに起因した表面欠陥の発生が極めて少ない表面性状
に優れた薄鋼板の得られることを見出した。熱延後、冷
間圧延、表面処理を行っても本発明の効果は損なわれ
ず、薄鋼板には、冷延鋼板、表面処理鋼板も含むものと
する。Means for Solving the Problems In order to solve the above-mentioned problems, the present inventors have studied the composition of steel materials and various conditions from casting by a continuous casting machine to hot rolling. After casting the steel, hold it for a certain period of time, then perform bending deformation while controlling the surface temperature, strain rate on the surface,
It has been found that, when the rolling conditions in the rough rolling are specified, a thin steel sheet excellent in surface properties with extremely few surface defects caused by cracks in hot rolling can be obtained. Even if cold rolling and surface treatment are performed after hot rolling, the effects of the present invention are not impaired, and the thin steel sheet includes a cold-rolled steel sheet and a surface-treated steel sheet.
【０００９】本発明はこれらの知見を基に更に検討を加
えてなされたものであり、すなわち、本発明は、 １． 以下の工程を備えたことを特徴とする表面性状に
優れた薄鋼板の製造方法。The present invention has been made based on these findings and further studied. That is, the present invention provides: A method for producing a thin steel sheet having excellent surface properties, comprising the following steps.
【００１０】（１）質量％で、Ｃ：０．２％以下、Ｓ
ｉ：１％以下、Ｍｎ：０．４〜２％、Ｐ：０．０８％以
下、Ｏ：０．００５％以下、Ｓ：０．０３％以下、Ｎ：
０．０１％以下、Ｓｎ：０．００４％以下を含有する鋼
を連続鋳造機により鋳造する工程。(1) In mass%, C: 0.2% or less, S
i: 1% or less, Mn: 0.4 to 2%, P: 0.08% or less, O: 0.005% or less, S: 0.03% or less, N:
Casting a steel containing 0.01% or less and Sn: 0.004% or less by a continuous casting machine.
【００１１】（２）鋳造後、鋳片表面の温度：９５０〜
１１５０℃において５分以上保持する工程。(2) After casting, the temperature of the slab surface: 950-
A step of holding at 1150 ° C. for 5 minutes or more.
【００１２】（３）鋳片の表面温度が、８５０℃未満、
７５０℃超え、となる温度域を避けて、表面での歪速度
が１×１０−４〜１×１０−１となる曲げ変形を行う工
程。(3) The surface temperature of the slab is less than 850 ° C.
A step of performing a bending deformation such that the strain rate on the surface is 1 × 10 −4 to 1 × 10 −1 , avoiding a temperature range exceeding 750 ° C.
【００１３】（４）粗圧延において、幅方向の圧下後、
歪速度１／秒以上で板厚方向の圧下を1回以上行う工
程。(4) In the rough rolling, after reduction in the width direction,
A step of reducing the thickness in the thickness direction at least once at a strain rate of 1 / second or more.
【００１４】２． 連続鋳造機における鋳造速度を１．
５ｍ／ｍｉｎ以上とする１記載の表面性状に優れた薄鋼
板の製造方法。2. The casting speed in the continuous casting machine was set to 1.
3. The method for producing a thin steel sheet having excellent surface properties according to item 1, which is at least 5 m / min.
【００１５】[0015]
【発明の実施の形態】本発明では、鋼組成、直送圧延プ
ロセスにおける連続鋳造後から、熱間圧延までの諸条件
について規定する。DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention specifies the steel composition and various conditions from continuous casting in a direct rolling process to hot rolling.
【００１６】１．鋼組成 Ｃ Ｃは鋼板の強度を確保するため添加する。０．２０％を
超えると加工性が劣化するため、０．２０％以下とす
る。表面欠陥低減のために好ましいＣ量は０．１０％以
下、より好ましくは０．０６％以下とする。1. Steel composition C C is added to secure the strength of the steel sheet. If it exceeds 0.20%, the workability deteriorates, so the content is made 0.20% or less. A preferable C amount for reducing surface defects is 0.10% or less, more preferably 0.06% or less.
【００１７】図１に熱間加工性に及ぼすＣ量の影響を示
す。Ｃ量の低下に伴い、８００℃近傍における絞り値の
劣化度は減少し、熱間加工性が改善されている。FIG. 1 shows the effect of the amount of carbon on hot workability. As the amount of C decreases, the degree of deterioration of the aperture value at around 800 ° C. decreases, and the hot workability is improved.
【００１８】Ｓｉ Ｓｉは固溶強化元素であり、鋼板の強度を確保するため
に添加する。１％を超えると表面性状が劣化するため、
１％以下とする。Si Si is a solid solution strengthening element and is added to secure the strength of the steel sheet. If it exceeds 1%, the surface properties will deteriorate,
1% or less.
【００１９】Ｍｎ Ｍｎは、連続鋳造時のスラブ表面または、スラブ表層下
での割れの発生抑制に有効な元素であり添加する。０．
４％未満では、その効果が得られず、一方、２％を超え
て含有すると加工性が劣化するため、０．４〜２％
（０．４％以上、２％以下）とする。Mn Mn is an element that is effective in suppressing the occurrence of cracks on the slab surface or under the slab surface during continuous casting, and is added. 0.
If the content is less than 4%, the effect cannot be obtained. On the other hand, if the content exceeds 2%, the workability deteriorates.
(0.4% or more and 2% or less).
【００２０】Ｐ Ｐは、連続鋳造時のスラブ表面または、スラブ表層下に
割れを発生し易くする有害な元素である。０．０８％を
超えると連続鋳造時のスラブ表面または、スラブ表層下
での割れの発生が著しくなり、熱間圧延での割れの発生
頻度が高くなるため、０．０８％以下とする。尚、より
好ましくは０．０２％以下とする。PP is a harmful element that easily causes cracks on the slab surface or under the slab surface during continuous casting. When the content exceeds 0.08%, cracks are remarkably generated on the slab surface or under the surface layer of the slab during continuous casting, and the frequency of occurrence of cracks during hot rolling increases. In addition, it is more preferably at most 0.02%.
【００２１】Ｏ Ｏは、連続鋳造時のスラブ表面または、スラブ表層下で
の割れの発生を抑制するため、０．００５％以下とす
る。O 2 O is set to 0.005% or less in order to suppress the occurrence of cracks on the slab surface or under the slab surface during continuous casting.
【００２２】Ｓ Ｓは、連続鋳造時のスラブ表面または、スラブ表層下に
割れを発生し易くする有害な元素であり、スラブに割れ
がない場合でも、熱間圧延時に割れを誘発する。S S is a harmful element that tends to cause cracking on the slab surface or under the slab surface during continuous casting, and induces cracking during hot rolling even if the slab has no crack.
【００２３】０．０３％を超えると連続鋳造時のスラブ
表面または、スラブ表層下での割れの発生が著しくな
り、熱間圧延での割れの発生頻度が高くなるため、０．
０３％以下とする。尚、より好ましくは０．０１％以下
で、更に好ましくは０．００５％以下とする。If the content exceeds 0.03%, cracks are remarkably generated on the slab surface or under the surface layer of the slab during continuous casting, and the frequency of cracks during hot rolling increases.
03% or less. Note that the content is more preferably 0.01% or less, and still more preferably 0.005% or less.
【００２４】Ｎ Ｎは、熱間圧延時の割れの発生を抑制するため、０．０
１％以下とする。 Ｓｎ Ｓｎは、連続鋳造時のスラブ表面または、スラブ表層下
に割れを著しく発生し易くする極めて有害な元素であ
り、０．００４％を超えると特にその傾向が強くなるた
め、０．００４％以下とする。NN is set to 0.0% to suppress the occurrence of cracks during hot rolling.
1% or less. Sn Sn is a very harmful element that easily causes cracks on the slab surface or under the slab surface layer during continuous casting. If it exceeds 0.004%, the tendency is particularly strong, so that Sn is 0.004% or less. And
【００２５】本発明での鋼の基本成分組成は以上である
が、更に強度特性を向上させるため、必要に応じて、Ｔ
ｉ，Ｎｂ、Ｖ，Ｍｏの一種又は二種以上の合計で、０．
０１〜０．２％、Ｃｕ：０．０２〜２％、Ｂ：０．００
０１〜０．０１％の一種又は二種以上を添加することが
できる。The basic composition of the steel according to the present invention is as described above. However, in order to further improve the strength characteristics, if necessary, T
One or more of i, Nb, V, and Mo, and
01-0.2%, Cu: 0.02-2%, B: 0.00
One or two or more of 0.01 to 0.01% can be added.
【００２６】２．製造条件 鋳造後、鋳片表面の温度：９５０〜１１５０℃において
５分以上保持する工程本発明では、熱間加工性を向上さ
せるため、連鋳機による鋳造後、鋳片表面温度が９５０
〜１１５０℃の範囲内で、５分以上保持する。2. Manufacturing conditions: Step of maintaining the slab surface at 950 to 1150 ° C. for 5 minutes or more after casting In the present invention, in order to improve hot workability, the slab surface temperature is 950 after casting by a continuous casting machine.
The temperature is kept within a range of １1150 ° C. for 5 minutes or more.
【００２７】鋳片の表面温度が、８５０℃未満、７５０
℃超え、となる温度域を避けて、表面での歪速度が１×
１０−４〜１×１０−１となる曲げ変形を行う工程 本発明では、曲げ変形による表面割れを抑制するため、
熱間脆性域となる、８５０℃未満、７５０℃超えの温度
域を避けて、表面での歪速度が１×１０−４〜１×１０
−１となるように曲げ変形を行う。When the surface temperature of the slab is less than 850 ° C. and 750
Exceeding the temperature range exceeding ℃, the strain rate on the surface is 1 ×
Step of performing bending deformation to be 10 −4 to 1 × 10 −1 In the present invention, in order to suppress surface cracking due to bending deformation,
Avoiding a temperature range of less than 850 ° C. and a temperature exceeding 750 ° C., which is a hot brittleness range, the strain rate on the surface is 1 × 10 −4 to 1 × 10
Bending deformation is performed so as to be −1 .
【００２８】粗圧延において、幅方向の圧下後、歪速度
１／秒以上で板厚方向の圧下を1回以上行う工程。In the rough rolling, a step of performing rolling in the sheet thickness direction at least once at a strain rate of 1 / second or more after rolling in the width direction.
【００２９】仕上圧延前に、材料表面、特にコーナ部で
の組織を微細化し、割れの発生を抑制するため、本発明
では、粗圧延において、幅殺し圧下後、歪速度１／秒以
上で水平圧下を1回以上行う。幅殺し圧下は、好ましく
は歪速度１／秒以上とする。Before the finish rolling, the surface of the material, especially at the corners, is refined to suppress the occurrence of cracks. Reduce at least once. The width reduction is preferably set to a strain rate of 1 / second or more.
【００３０】尚、本発明では連続鋳造機の型式は規定せ
ず、湾曲型連鋳機、垂直曲げ型連鋳機等に適用すること
が可能である。高能率で鋳片の温度低下を抑制し直送圧
延を可能とするためには、鋳造速度は、１．５ｍ／ｍｉ
ｎ以上とすることが好ましい。In the present invention, the type of the continuous casting machine is not specified, and the invention can be applied to a curved continuous casting machine, a vertical bending continuous casting machine and the like. In order to suppress the temperature drop of the slab at a high efficiency and enable direct rolling, the casting speed is 1.5 m / mi.
It is preferable to set it to n or more.
【００３１】また、粗圧延は、曲げ変形後、一旦冷却
し、再加熱後に行うか、又は冷却することなく直接行う
ことが可能で特に規定しない。The rough rolling is not particularly limited, since it can be cooled once after bending deformation, and then can be performed after reheating, or can be directly performed without cooling.
【００３２】[0032]
【実施例】表１に示す化学成分を有する鋼Ａ，Ｂ，Ｃを
転炉で溶製後、鋳造、粗圧延、仕上圧延により熱延コイ
ルとした。その後、表面検査により、表面欠陥の有無を
調査した。表２に製造条件、評価結果を示す。EXAMPLES Steels A, B, and C having the chemical components shown in Table 1 were melted in a converter and cast, rough-rolled, and finish-rolled to form hot-rolled coils. Thereafter, the presence or absence of surface defects was examined by surface inspection. Table 2 shows the manufacturing conditions and evaluation results.
【００３３】表２において本発明例であるＮｏ．１〜３
は、表面欠陥は検出されず、優れた表面性状を有してい
る。一方、比較例であるＮｏ．４〜６は、鋳片の保持時
間、曲げ変形時の表面温度および粗圧延条件のいずれか
が本発明範囲外であり、表面欠陥の発生が認められた。In Table 2, No. 1 of the present invention was used. 1-3
No surface defects were detected, and excellent surface properties were obtained. On the other hand, in Comparative Example No. In Nos. 4 to 6, any of the holding time of the slab, the surface temperature at the time of bending deformation, and the rough rolling conditions were out of the range of the present invention, and generation of surface defects was recognized.
【００３４】[0034]
【表１】 [Table 1]
【００３５】[0035]
【表２】 [Table 2]
【００３６】[0036]
【発明の効果】本発明は、鋳片の保持時間、曲げ変形時
の表面温度、及び歪速度を調整し、更に粗圧延において
幅方向の圧下後、板厚方向の圧下をすることにより、熱
間圧延での割れに起因した表面欠陥の発生が極めて少な
い表面性状に優れた薄鋼板およびその製造方法が得ら
れ、産業上極めて有用である。According to the present invention, the holding time of the slab, the surface temperature during bending deformation, and the strain rate are adjusted, and further, in the rough rolling, after the reduction in the width direction, the reduction in the sheet thickness direction is achieved. A thin steel sheet excellent in surface properties, in which generation of surface defects due to cracks in cold rolling is extremely small, and a method for producing the same are obtained, and are extremely useful in industry.
【図１】熱間加工性（高温引張試験における絞り値）に
及ぼすＣ量の影響を示す図。FIG. 1 is a view showing the effect of the amount of carbon on hot workability (a drawn value in a high-temperature tensile test).
Claims (2)
面性状に優れた薄鋼板の製造方法。 （１）質量％で、Ｃ：０．２％以下、Ｓｉ：１％以下、
Ｍｎ：０．４〜２％、Ｐ：０．０８％以下、Ｏ：０．０
０５％以下、Ｓ：０．０３％以下、Ｎ：０．０１％以
下、Ｓｎ：０．００４％以下を含有する鋼を連続鋳造機
により鋳造する工程。 （２）鋳造後、鋳片表面の温度：９５０〜１１５０℃に
おいて５分以上保持する工程。 （３）鋳片の表面温度が、８５０℃未満、７５０℃超
え、となる温度域を避けて、表面での歪速度が１×１０
−４〜１×１０−１となる曲げ変形を行う工程。 （４）粗圧延において、幅方向の圧下後、歪速度１／秒
以上で板厚方向の圧下を1回以上行う工程。1. A method for producing a thin steel sheet having excellent surface properties, comprising the following steps. (1) In mass%, C: 0.2% or less, Si: 1% or less,
Mn: 0.4 to 2%, P: 0.08% or less, O: 0.0
Casting a steel containing not more than 05%, not more than 0.03% of S, not more than 0.01% of N, not more than 0.004% of Sn by a continuous casting machine. (2) A step of holding the slab surface at 950 to 1150 ° C. for 5 minutes or more after casting. (3) The strain rate on the surface is 1 × 10, avoiding a temperature range in which the surface temperature of the slab is less than 850 ° C. or more than 750 ° C.
Step of performing bending deformation to be −4 to 1 × 10 −1 . (4) In the rough rolling, after the reduction in the width direction, a step of performing the reduction in the thickness direction at least once at a strain rate of 1 / second or more.
／ｍｉｎ以上とする請求項１記載の表面性状に優れた薄
鋼板の製造方法。2. The casting speed in a continuous casting machine is 1.5 m.
The method for producing a thin steel sheet having excellent surface properties according to claim 1, wherein the rate is not less than / min.
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| JP2000224324A JP4696341B2 (en) | 2000-07-25 | 2000-07-25 | Manufacturing method of thin steel sheet with excellent surface properties |
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|---|---|---|---|
| JP2000224324A JP4696341B2 (en) | 2000-07-25 | 2000-07-25 | Manufacturing method of thin steel sheet with excellent surface properties |
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| Publication Number | Publication Date |
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| JP2002035805A true JP2002035805A (en) | 2002-02-05 |
| JP4696341B2 JP4696341B2 (en) | 2011-06-08 |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20120037277A1 (en) * | 2009-04-06 | 2012-02-16 | Tomoji Kumano | Method of treating steel for grain-oriented electrical steel sheet and method of manufacturing grain-oriented electrical steel sheet |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60262915A (en) * | 1984-06-11 | 1985-12-26 | Sumitomo Metal Ind Ltd | Method for preventing surface cracking of continuous cast billet |
| JPS6240960A (en) * | 1985-08-19 | 1987-02-21 | Sumitomo Metal Ind Ltd | Method for preventing crack in hot direct rolling stage of steel ingot |
| JPH0776375B2 (en) * | 1986-03-13 | 1995-08-16 | 住友金属工業株式会社 | Hot rolling method that prevents surface cracking of billets |
-
2000
- 2000-07-25 JP JP2000224324A patent/JP4696341B2/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60262915A (en) * | 1984-06-11 | 1985-12-26 | Sumitomo Metal Ind Ltd | Method for preventing surface cracking of continuous cast billet |
| JPS6240960A (en) * | 1985-08-19 | 1987-02-21 | Sumitomo Metal Ind Ltd | Method for preventing crack in hot direct rolling stage of steel ingot |
| JPH0776375B2 (en) * | 1986-03-13 | 1995-08-16 | 住友金属工業株式会社 | Hot rolling method that prevents surface cracking of billets |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20120037277A1 (en) * | 2009-04-06 | 2012-02-16 | Tomoji Kumano | Method of treating steel for grain-oriented electrical steel sheet and method of manufacturing grain-oriented electrical steel sheet |
| US8202374B2 (en) * | 2009-04-06 | 2012-06-19 | Nippon Steel Corporation | Method of treating steel for grain-oriented electrical steel sheet and method of manufacturing grain-oriented electrical steel sheet |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4696341B2 (en) | 2011-06-08 |
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