JPH0953123A - Production of hot rolled steel plate excellent in workability - Google Patents
Production of hot rolled steel plate excellent in workabilityInfo
- Publication number
- JPH0953123A JPH0953123A JP7206229A JP20622995A JPH0953123A JP H0953123 A JPH0953123 A JP H0953123A JP 7206229 A JP7206229 A JP 7206229A JP 20622995 A JP20622995 A JP 20622995A JP H0953123 A JPH0953123 A JP H0953123A
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- rolling
- hot
- rolled steel
- point
- stage
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- 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.)
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- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、加工性に優れた熱
延鋼板を低コストで製造する方法に関わり、その用途
は、自動車、家電、建材、容器等である。また、これを
冷間圧延用の素材として用いることも可能である。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a hot-rolled steel sheet having excellent workability at low cost, and its applications are automobiles, home appliances, building materials, containers and the like. It is also possible to use this as a material for cold rolling.
【０００２】[0002]
【従来の技術】近年、自動者用鋼板に代表される加工用
鋼板の分野においては、素材費削減の観点から、従来よ
り用いられてきた冷延鋼板に代わって、薄手熱延鋼板の
需要が増加しつつする。しかしながら、このような薄手
熱延鋼板においては、圧延時の冷却が著しく速く進行す
るため、仕上げ温度がＡｒ3 変態点（以下、Ａｒ3 点）
を大きく下回ることが多く、伸びの劣化、材質特性の異
方性、操業の不安定性等の問題の原因となっていた。2. Description of the Related Art In recent years, in the field of processing steel sheets represented by steel sheets for automatic operators, from the viewpoint of material cost reduction, there has been a demand for thin hot-rolled steel sheets instead of cold-rolled steel sheets that have been used conventionally. To increase. However, in such a thin hot-rolled steel sheet, cooling during rolling progresses remarkably quickly, so that the finishing temperature is Ar 3 transformation point (hereinafter, Ar 3 point).
In many cases, it was a cause of problems such as deterioration of elongation, anisotropy of material properties, and instability of operation.
【０００３】このような問題を改善すべく、Ａｒ3 点を
低下させる目的でＢを添加した熱延鋼板が開発されてい
る。特開昭６３−７６８２２号公報は、その代表的な技
術で、極低炭素鋼あるいは、低炭素鋼に０．００１５〜
０．００４５％のＢを添加し、仕上げ温度をＡｒ3 点以
上とすることにより、優れた加工性を有する熱延鋼板を
得るものである。In order to improve such problems, hot rolled steel sheets containing B have been developed for the purpose of lowering the Ar 3 point. Japanese Unexamined Patent Publication (Kokai) No. 63-76822 discloses a typical technique of ultra low carbon steel or low carbon steel with 0.0015-
By adding 0.0045% of B and setting the finishing temperature at the Ar 3 point or higher, a hot-rolled steel sheet having excellent workability is obtained.
【０００４】また、特開昭６３−２１６９２５号公報、
特開昭６３−１４３２２４号公報、特開昭６３−１４３
２２５号公報には、Ｂの効果を助長する技術として、Ｔ
ｉやＮｂを添加する方法や熱延加熱温度を限定する方法
についての開示がある。さらに、特開平２−１０４６１
４号公報には、Ｂ添加鋼における材質の異方性を改善す
るために、仕上げ圧延の最終スタンドでの圧下率を規定
する技術が開示されている。Further, Japanese Patent Laid-Open No. 63-216925,
JP-A-63-143224, JP-A-63-143
No. 225 discloses that as a technique for promoting the effect of B, T
There is a disclosure of a method of adding i or Nb and a method of limiting a hot rolling heating temperature. Furthermore, JP-A-2-10461
Japanese Unexamined Patent Publication No. 4 (1994) discloses a technique of defining a reduction ratio at the final stand of finish rolling in order to improve the material anisotropy in the B-added steel.
【０００５】このようにＢはＡｒ3 点を低下させるた
め、熱延の仕上げ温度をＡｒ3 点以上とすることによ
り、板厚方向に均一な組織を得ることが可能となる。し
かしながら、Ｂの効果は、熱間圧延の最終仕上げ条件の
みならず、圧延途中の製造条件によって大きく変化する
ことが新たに明らかとなった。As described above, since B lowers the Ar 3 point, it is possible to obtain a uniform structure in the plate thickness direction by setting the hot rolling finishing temperature to be the Ar 3 point or higher. However, it was newly revealed that the effect of B greatly changes not only in the final finishing conditions of hot rolling but also in the manufacturing conditions during rolling.
【０００６】[0006]
【発明が解決しようとする課題】従来の薄手熱延鋼板に
おいては、板厚が薄いために冷却が速く進行し、熱延仕
上げ温度がＡｒ3 点を大きく下回り、加工性の劣化を招
いたり、操業を不安定にする要因となっていた。本発明
の目的は、ＢによるＡｒ3 点の低下量を従来よりも大き
くさせることにより、加工性に優れた薄手熱延鋼板を安
定して得るための製造方法を提供することにある。In the conventional thin hot-rolled steel sheet, since the sheet thickness is thin, cooling progresses rapidly, and the hot-rolling finishing temperature is much lower than Ar 3 point, which causes deterioration of workability. It was a factor that made the operation unstable. An object of the present invention is to provide a manufacturing method for stably obtaining a thin hot-rolled steel sheet having excellent workability by increasing the amount of decrease in Ar 3 point by B as compared with the conventional method.
【０００７】[0007]
【課題を解決するための手段】本発明による加工性に優
れた熱延鋼板の製造方法は以下の通りである。 （１）重量％で、Ｃ＝０．０１〜０．１５％、Ｍｎ＝
０．０３〜２．０％、Ｓｉ≦０．５％、Ａｌ＝０．００
３〜０．２％、Ｐ≦０．１０％、Ｓ≦０．０２％、Ｎ≦
０．００７％、Ｂ≦０．００１５超〜０．０１％を満た
す範囲で含有し、残部は鉄および不可避的不純物よりな
るスラブの熱間圧延に際し、Ｘ段からなる仕上げ熱延機
の（Ｘ−４）段目および（Ｘ−３）段目の圧延を、８４
０℃以上９４０℃未満の温度範囲で、かつそこでの圧下
率で合計で６０％以上とし、（Ｘ−２）と（Ｘ−１）段
目の圧下率を合計で４５％以下とし、最終仕上げ圧延温
度を（Ａｒ3 点−２０℃）以上とすることを特徴とする
加工性に優れた熱延鋼板の製造方法。The method for producing a hot-rolled steel sheet having excellent workability according to the present invention is as follows. (1)% by weight, C = 0.01 to 0.15%, Mn =
0.03-2.0%, Si ≦ 0.5%, Al = 0.00
3 to 0.2%, P ≦ 0.10%, S ≦ 0.02%, N ≦
0.007% and B ≦ 0.0015 to 0.01% are contained in the range with the balance being iron and unavoidable impurities during slab hot rolling. -4) rolling of the 4th stage and (X-3) stage, 84
In the temperature range of 0 ° C. or higher and lower than 940 ° C., and the reduction ratio thereat is 60% or more in total, and the reduction ratios of the (X-2) and (X-1) stages are 45% or less in total, and final finishing is performed. A method for producing a hot-rolled steel sheet excellent in workability, which comprises setting a rolling temperature to (Ar 3 point −20 ° C.) or higher.
【０００８】（２）さらに重量％で、Ｔｉ＝０．００３
〜０．０５％、Ｎｂ＝０．００３〜０．０５％のうち１
種または２種を含有することを特徴とする上記（１）記
載の加工性に優れた熱延鋼板の製造方法。 （３）粗圧延した粗バーをコイル状に巻取った後、巻戻
し、巻終わり端より連続的に仕上げ熱延を行うことを特
徴とする上記（１）または（２）記載の加工性に優れた
熱延鋼板の製造方法。(2) Further, in weight%, Ti = 0.003
~ 0.05%, Nb = 0.003 to 1 out of 0.05%
Type or two types are contained, The manufacturing method of the hot-rolled steel sheet excellent in workability of the said (1) description characterized by the above-mentioned. (3) The workability according to the above (1) or (2), characterized in that after the rough rolled rough bar is wound into a coil, it is rewound and continuously finish hot rolled from the end of winding. Excellent hot rolled steel sheet manufacturing method.
【０００９】（４）粗圧延した粗バーをコイル状に巻取
った後、巻戻し、その巻終わり端と先行する粗バーの末
端とを接合し、連続的に仕上げ熱延を行うことを特徴と
する上記（１）または（２）記載の加工性に優れた熱延
鋼板の製造方法。(4) Characteristically, after the roughly rolled rough bar is wound into a coil, it is rewound, the end of the winding is joined to the end of the preceding rough bar, and finish hot rolling is continuously performed. The method for producing a hot-rolled steel sheet having excellent workability according to (1) or (2) above.
【００１０】本発明における熱延鋼板の製造方法は、Ｃ
量，Ｂ量、さらに仕上げ熱延中の圧下配分を限定するこ
とにより、Ａｒ3 点を効率的に低下させることにより加
工性に優れた熱延鋼板を製造するものである。以下に本
発明における限定理由を述べる。The method for producing a hot rolled steel sheet according to the present invention is C
By limiting the amount, the amount of B, and the reduction distribution during finish hot rolling, the hot rolled steel sheet excellent in workability is manufactured by efficiently lowering the Ar 3 point. The reasons for limitation in the present invention will be described below.
【００１１】まず化学成分の限定理由について述べる。
Ｃは、本発明において最も重要な元素の１つである。Ｃ
は、単独またはＢとの複合添加によって、Ａｒ3 点を低
下させる効果を有する。したがって、０．０１％以上添
加する。０．０１％未満の添加では、Ａｒ3 点を低下さ
せる効果が顕著でなく、また、脱炭コストの上昇を招
く。一方、Ｃが０．１５％を超えると加工性や時効性の
劣化を招くので、これを上限とする。Ａｒ3 点を低下さ
せ、優れた加工性を確保するために好ましいＣの範囲
は、０．０２超〜０．０８％未満である。First, the reasons for limiting the chemical components will be described.
C is one of the most important elements in the present invention. C
Has the effect of lowering the Ar 3 point, either alone or in combination with B. Therefore, 0.01% or more is added. If it is added in an amount of less than 0.01%, the effect of lowering the Ar 3 point is not remarkable, and the decarburization cost is increased. On the other hand, if C exceeds 0.15%, workability and aging are deteriorated, so this is made the upper limit. A preferable range of C is 0.02 to less than 0.08% in order to reduce the Ar 3 point and ensure excellent workability.
【００１２】Ｓｉは、その量の増加にともなって降伏強
度が上昇し、伸びが低下し、Ａｒ3点を上昇させ、表面
スケール起因の疵を誘発し、さらにメッキ性を損なうの
で０．５％以下とする。さらに優れた表面性状を確保
し、Ａｒ3 点を高くせず、優れた延性を得るための好ま
しい範囲は０．０５％以下である。Si increases the yield strength, decreases elongation, raises the Ar 3 point, induces flaws due to surface scale, and impairs the plating property with an increase in the amount of Si. Below. A preferable range is 0.05% or less in order to secure further excellent surface properties, not to raise the Ar 3 point, and to obtain excellent ductility.
【００１３】Ｍｎは、Ａｒ3 点を低下させるのに有効な
元素であるので、積極的に添加してもよい。ただし、
２．０％を超えると合金コストが著しく上昇し、伸びや
メッキ性の劣化を招くのでこれを上限とする。また、
０．０３％未満では、固溶Ｓに基づく熱間脆化を誘発
し、また製鋼コストを上昇させるので、これを下限とす
る。特にＡｒ3 点を著しく低下させたり、強度を高める
必要がない場合には、０．１０超〜０．７０％未満が好
ましい範囲である。Since Mn is an element effective in lowering the Ar 3 point, it may be positively added. However,
If it exceeds 2.0%, the alloy cost will remarkably increase, and the elongation and the deterioration of the plating property will be caused, so this is made the upper limit. Also,
If it is less than 0.03%, hot embrittlement based on solid solution S is induced and the steelmaking cost is increased, so this is made the lower limit. Particularly, when it is not necessary to remarkably reduce the Ar 3 point or increase the strength, the range of more than 0.10 to less than 0.70% is a preferable range.
【００１４】Ｐは、偏析の激しい元素であるため、０．
１０％超では熱間割れの原因となり、２次加工性も著し
く阻害される。さらに、Ａｒ3 点も上昇してしまう。ま
た、溶融亜鉛メッキの合金化速度が著しく遅滞化される
ため０．１０％以下とする。したがって、特に強度を上
昇させる必要のない場合には、０．０３％以下が適正な
範囲である。Since P is an element which is highly segregated, P.
If it exceeds 10%, hot cracking is caused, and the secondary workability is significantly impaired. Furthermore, the Ar 3 point also rises. Further, since the alloying rate of hot dip galvanization is significantly delayed, it is set to 0.10% or less. Therefore, if it is not necessary to increase the strength in particular, 0.03% or less is an appropriate range.
【００１５】Ｓは、その添加量を０．０２％以下とす
る。Ｓ量が０．０２％超では、熱間割れが生じ易くな
る。優れた延性を確保し、また、ＭｎがＡｒ3 点を低下
させる効果を助長するためのＳの好ましい範囲は０．０
１０％以下である。The addition amount of S is 0.02% or less. If the amount of S exceeds 0.02%, hot cracking tends to occur. The preferable range of S for securing excellent ductility and promoting the effect of Mn lowering the Ar 3 point is 0.0.
It is 10% or less.
【００１６】Ａｌは、少なくとも０．００３％を添加す
る。Ａｌが０．００３％未満では、ＮがＡｌＮ以外にＢ
Ｎを形成してしまい、Ｂの効果が低下する。しかし、
０．２％を超えるとコストアップとなるばかりか介在物
の増加を招き、加工性を劣化させる。Ｂの効果をさらに
顕著にするための好ましい範囲は０．０１〜０．１％で
ある。At least 0.003% of Al is added. When Al is less than 0.003%, N is B in addition to AlN.
N is formed and the effect of B is reduced. But,
If it exceeds 0.2%, not only the cost is increased, but also inclusions are increased and the workability is deteriorated. The preferable range for further enhancing the effect of B is 0.01 to 0.1%.
【００１７】Ｎは、その増加とともにＡｌ等の窒化物形
成元素を増量しなければならずコスト高となるし、ＢＮ
として析出するＢ量が増加し、Ａｒ3 点を低下させるの
に有効な固溶Ｂ量が減ってしまうので少ないほど望まし
い。したがって、０．００７％以下とする。Ｂの低Ａｒ
3 化効果を助長するためには、Ｎは０．００２５％未満
とするのが好ましい。As N increases in amount, the amount of nitride forming elements such as Al must be increased, resulting in high cost.
As a result, the amount of B that precipitates increases and the amount of solid solution B that is effective for lowering the Ar 3 point decreases. Therefore, it is set to 0.007% or less. B low Ar
In order to promote the effect of 3 conversion, N is preferably less than 0.0025%.
【００１８】Ｂは、本発明において最も重要な元素の１
つである。Ｂは、Ｃとの複合添加によって、Ａｒ3 点を
顕著に低下させる効果を有する。したがって、０．００
１５％超添加する。０．００１５％以下の添加では、Ａ
ｒ3 点を低下させる効果が顕著でなく、Ａｒ3 点を８３
０℃以下とすることが困難となる。一方、Ｂが０．０１
％を超えると加工性の劣化を招くので、これを上限とす
る。Ａｒ3 点を充分に低減させ、優れた加工性を確保す
るために好ましいＢの範囲は、０．００２０超〜０．０
０５０％未満である。B is one of the most important elements in the present invention.
One. B has the effect of significantly decreasing the Ar 3 point by the combined addition of C. Therefore, 0.00
Add more than 15%. If 0.0015% or less is added, A
The effect of lowering the r 3 point is not remarkable, and the Ar 3 point is 83
It becomes difficult to keep the temperature below 0 ° C. On the other hand, B is 0.01
If it exceeds%, workability is deteriorated, so this is made the upper limit. In order to sufficiently reduce the Ar 3 point and ensure excellent workability, the preferable range of B is more than 0.0020 to 0.0.
It is less than 050%.
【００１９】さらに、ＢとＣは、Ｂ（％）×Ｃ（％）
が、４×１０-5以上となるように添加することが望まし
い。すなわち、ＢやＣは、いずれもＡｒ3 点を低下させ
る元素であるが、両者が複合添加されてより顕著な効果
を発現するからである。Ｂ（％）×Ｃ（％）＞８×１０
-4がさらに好ましい範囲である。Further, B and C are B (%) × C (%)
However, it is desirable to add so as to be 4 × 10 −5 or more. That is, B and C are both elements that lower the Ar 3 point, but when both are added in combination, a more remarkable effect is exhibited. B (%) × C (%)> 8 × 10
-4 is a more preferable range.
【００２０】Ｔｉ，Ｎｂは、０．００３〜０．０５％の
範囲で添加してもよい。Ｔｉ，Ｎｂはそれ自身がＡｒ3
点を低下させる効果を有する他、Ｎを化合物として固定
する効果を有し、ＢＮとして析出するＢ量を減少させる
ことを通じてＡｒ3 点を低下させる。０．００３％未満
の添加では、Ａｒ3 点を低下させる効果が充分ではな
く、０．０５％超添加しても大きな効果はなく、微細析
出物が増加し、加工性を劣化させたり、コストアップを
招くのでこれを上限とする。Ｂの低Ａｒ3 化効果を発現
させ、優れた加工性を得るためには０．００５超〜０．
０２５％未満がより好ましい範囲である。さらに、Ａｒ
3 点を低下させる元素である、Ｃｒ，Ｎｉ，Ｃｕ，Ｖ，
Ｍｏ，Ｚｒ，Ｗを１種類以上合計で１％以下添加しても
よい。Ti and Nb may be added in the range of 0.003 to 0.05%. Ti and Nb are themselves Ar 3
In addition to the effect of lowering the point, it also has the effect of fixing N as a compound and lowers the Ar 3 point by reducing the amount of B precipitated as BN. If it is added less than 0.003%, the effect of lowering the Ar 3 point is not sufficient, and if it is added more than 0.05%, there is no great effect, and fine precipitates increase, the workability deteriorates, and the cost is reduced. This is an upper limit, so this is the upper limit. In order to exert the Ar 3 lowering effect of B and obtain excellent workability, it exceeds 0.005 to 0.
Less than 025% is a more preferable range. Furthermore, Ar
Cr, Ni, Cu, V, which are elements that lower the three points
One or more kinds of Mo, Zr and W may be added in a total amount of 1% or less.
【００２１】上記成分を得るための原料は特に限定しな
いが、鉄鉱石を原料として、高炉転炉法により成分を調
製する方法以外にスクラップを原料としてもよいし、こ
れを電気炉で溶製してもよい。スクラップを原料の全部
または一部として使用する際には、Ｃｕ，Ｃｒ，Ｎｉ，
Ｓｎ，Ｓｂ，Ｚｎ，Ｐｂ，Ｍｏ等のトランプエレメント
を含有してもよい。The raw materials for obtaining the above-mentioned components are not particularly limited, but scraps may be used as raw materials other than the method of preparing the components by the blast furnace converter method using iron ore as the raw material. May be. When scrap is used as all or part of the raw material, Cu, Cr, Ni,
It may contain a playing card element such as Sn, Sb, Zn, Pb or Mo.
【００２２】次に製造プロセスに関する限定理由を述べ
る。熱間圧延に供するスラブは、特に限定するものでは
ない。すなわち、鋳型鋳造鋳塊、連続鋳造スラブや薄ス
ラブキャスターで製造したものなどであればよい。ま
た、鋳造後に直ちに熱間圧延を行う、連続鋳造−直接圧
延（ＣＣ−ＤＲ）のようなプロセスにも適合する。Next, the reasons for limitation regarding the manufacturing process will be described. The slab used for hot rolling is not particularly limited. That is, it may be a mold cast ingot, a continuously cast slab, or a thin slab caster. It is also suitable for processes such as continuous casting-direct rolling (CC-DR) in which hot rolling is performed immediately after casting.
【００２３】熱間圧延における加熱温度は、１０００〜
１３５０℃の範囲で、仕上げ熱延温度をＡｒ3 点以上と
するために必要な温度とすればよい。固溶Ｂを確保する
観点で、加熱温度は１２００℃超とすることが好まし
い。The heating temperature in hot rolling is from 1000 to
In the range of 1350 ° C., the temperature may be set to a temperature required to set the finish hot rolling temperature to the Ar 3 point or higher. From the viewpoint of securing the solid solution B, the heating temperature is preferably higher than 1200 ° C.
【００２４】熱間圧延の粗圧延終了後には、一度巻取っ
てもよい。このときの巻取り条件は特に限定するもので
はないが、曲率半径が２．０ｍ以下、１１００℃以下９
５０℃以上の温度で０．５秒以上保持するのがよい。こ
れによってＡｌＮ、さらにはＴｉ，Ｎｂを添加する際に
はＴｉＮ，ＮｂＮ等が析出、粗大化するため、ＢＮの形
成が抑制され、かつ材質も良好になる。After the rough rolling of the hot rolling is finished, it may be wound once. The winding conditions at this time are not particularly limited, but the radius of curvature is 2.0 m or less, 1100 ° C. or less 9
It is preferable to hold at a temperature of 50 ° C. or higher for 0.5 seconds or longer. As a result, TiN, NbN, etc. are precipitated and coarsened when AlN, and further Ti, Nb are added, so that the formation of BN is suppressed and the material becomes good.
【００２５】巻取り後は、加熱炉内で積極的に加熱して
もよいし、ボックス内で加熱を行わずに保温してもよい
し、単に大気中で巻取ってもよい。加熱炉や保温ボック
スを用いる際には雰囲気をアルゴンガス、窒素ガス、水
素ガス等あるいはこれらの混合ガス等の不活性雰囲気と
することも、優れた表面特性や板厚精度を確保する観点
で好ましい。このように粗バーを巻取った場合には、再
度巻戻し、巻戻し端より仕上げ圧延機に装入する。After winding, it may be positively heated in a heating furnace, may be kept warm in the box without heating, or may be simply wound in the atmosphere. When using a heating furnace or a heat-retaining box, it is also preferable to use an inert atmosphere such as argon gas, nitrogen gas, hydrogen gas or a mixed gas thereof as the atmosphere from the viewpoint of securing excellent surface characteristics and plate thickness accuracy. . When the rough bar is wound up in this way, it is rewound again and loaded into the finishing mill from the rewinding end.
【００２６】粗バーの巻取り、巻戻し後には、その先端
部と先行する粗バーの後端部とを接合して、連続的に仕
上げ熱延を行ってもよい。これによって、端部材質の劣
化によって生ずる歩留まりの低下を防止することができ
る。さらに、本発明の特徴である仕上げ中段の大圧下、
後段の軽圧下という条件のときには、特に連続熱延を行
うことで板厚精度や操業安定性が向上する。粗バーの接
合方法は特に限定されるものではないが、レーザー溶
接、アーク溶接、フラッシュバット溶接、圧接等で行う
のが好ましい。After winding and unwinding the rough bar, the leading end of the rough bar and the trailing end of the preceding rough bar may be joined together for continuous hot rolling. As a result, it is possible to prevent the yield from decreasing due to the deterioration of the end member quality. Furthermore, a large reduction in the finishing middle stage, which is a feature of the present invention,
Under the condition of light pressure reduction in the latter stage, the sheet thickness accuracy and operation stability are improved by performing continuous hot rolling in particular. The method of joining the coarse bars is not particularly limited, but laser welding, arc welding, flash butt welding, pressure welding or the like is preferable.
【００２７】熱間圧延における仕上げ圧延の条件は、本
発明において特に重要である。まず、Ｘ段（通常、Ｘは
６または７）からなる仕上げ圧延において、（Ｘ−４）
および（Ｘ−３）段目を８４０℃以上９４０℃未満の温
度域にて圧下率を合計で６０％以上とし、（Ｘ−２）と
（Ｘ−１）段目の圧下率を合計で４５％以下とすること
が必要である。The conditions of finish rolling in hot rolling are particularly important in the present invention. First, in finish rolling consisting of X stages (usually X is 6 or 7), (X-4)
In the temperature range of 840 ° C. or higher and lower than 940 ° C. in the (X-3) th stage, the total reduction rate is 60% or more, and the total reduction rate in the (X-2) and (X-1) stages is 45%. It is necessary to be less than or equal to%.
【００２８】ここで合計の圧下率Ｒ（％）とは、（Ｘ−
４）段手前の板厚ｔ１（mm）、（Ｘ−３）段直後の板厚
ｔ２（mm）とすると、Ｒ（％）＝（ｔ１−ｔ２）／ｔ１
×１００または、（Ｘ−４）段目の圧下率ｒ１（％）、
（Ｘ−３）段目の圧下率ｒ２（％）としたとき、Ｒ
（％）＝｛１−（１−ｒ１／１００）（１−ｒ２／１０
０）｝×１００と定義される。Here, the total reduction ratio R (%) is (X-
4) R (%) = (t1-t2) / t1 where t1 (mm) is the thickness before the step and (t-3) is the thickness immediately after the (X-3) step.
× 100 or (X-4) th stage rolling reduction r1 (%),
When the rolling reduction ratio of the (X-3) th stage is r2 (%), R
(%) = {1- (1-r1 / 100) (1-r2 / 10
0)} × 100.
【００２９】（Ｘ−４）および（Ｘ−３）段での圧下率
を大きくすることによりγの再結晶を促進させ、かつ結
晶粒成長を促すことにより、変態の核生成サイトである
結晶粒界面積が減じ、同時に結晶粒界のＢ濃度が高くな
ることでＡｒ3 点が顕著に低下すると思われる。圧下率
が合計で６０％未満ではこの効果が顕著ではない。By increasing the rolling reduction in the stages (X-4) and (X-3), the recrystallization of γ is promoted and the crystal grain growth is promoted. It is considered that the Ar 3 point is remarkably lowered due to the decrease of the interfacial area and the increase of the B concentration of the crystal grain boundary at the same time. This effect is not remarkable when the rolling reduction is less than 60% in total.
【００３０】さらに、（Ｘ−４）段と（Ｘ−３）段の合
計圧下率が一定の場合には、前段側、すなわち、（Ｘ−
４）段での圧下を高くする方がよい。これは前段側すな
わち所定の範囲内でより高温側で大圧下する方が再結
晶、粒成長の促進に有利であるためと思われる。（Ｘ−
４）段目の加工は４５％以上とすることが望ましい。ま
た、（Ｘ−４）と（Ｘ−３）段の圧延は８４０℃以上９
４０℃未満の温度域で行う。Further, when the total reduction ratio of the (X-4) th stage and the (X-3) th stage is constant, the preceding stage side, that is, (X-
4) It is better to increase the rolling reduction in the stage. It is considered that this is because it is more advantageous to promote recrystallization and grain growth when the large pressure reduction is performed on the front side, that is, on the higher temperature side within a predetermined range. (X-
4) It is desirable that the processing of the step is 45% or more. Further, the rolling of the (X-4) and (X-3) stages is 840 ° C or higher and 9
It is performed in a temperature range of less than 40 ° C.
【００３１】この温度が８４０℃未満では、γの再結
晶、粒成長が進行し難く、Ａｒ3 点が充分に低下せず、
仕上げ圧延途中でＡｒ3 点を大きく下回ってしまうた
め、優れた材質が確保できず、また、操業も不安定とな
る。一方、（Ｘ−４）と（Ｘ−３）段の温度が９４０℃
以上となると、動的回復により再結晶、粒成長が起こり
難くなる。γの再結晶、粒成長を促進するためには、８
６０℃以上９３０℃未満がさらに好ましい範囲である。If this temperature is lower than 840 ° C., recrystallization of γ and grain growth are difficult to proceed, and the Ar 3 point is not sufficiently lowered.
Since the Ar 3 point is greatly reduced during the finish rolling, an excellent material cannot be secured and the operation becomes unstable. On the other hand, the temperatures of the (X-4) and (X-3) stages are 940 ° C.
In the above cases, recrystallization and grain growth are less likely to occur due to dynamic recovery. To promote γ recrystallization and grain growth, 8
A more preferable range is 60 ° C or higher and lower than 930 ° C.
【００３２】仕上げ後段では温度が低いため、大圧下し
ても再結晶、粒成長が充分に進まなかったり、再結晶し
ても結晶粒径が著しく微細となりむしろＡｒ3 点が高く
なってしまう。したがって、（Ｘ−２）段および（Ｘ−
１）段の合計の圧下率を４５％以下の軽圧下とするのが
よい。このような仕上げ後段の軽圧下は、仕上げ中段で
形成された再結晶組織の粒成長を促す作用を有する他
に、操業の安定性にも効果がある。仕上げ中段で形成さ
れた組織の微細化を抑制するためには３５％以下とする
のがより効果的である。Since the temperature is low in the post-finishing stage, recrystallization and grain growth do not proceed sufficiently even under a large pressure, or the crystal grain size becomes remarkably fine even if recrystallized, and the Ar 3 point becomes rather high. Therefore, (X-2) stage and (X-
It is preferable that the total reduction ratio of 1) stage is 45% or less. The light reduction at the post-finishing stage has the effect of promoting the grain growth of the recrystallized structure formed at the mid-finishing stage, and is also effective for the stability of operation. In order to suppress the refinement of the structure formed in the middle stage of finishing, it is more effective to be 35% or less.
【００３３】仕上げ熱延中の８８０℃以下での冷却速度
は、３０℃/s超とするのが好ましい。３０℃/s以下で
は、たとえＣ量とＢ量が適当であっても、Ａｒ3 点が充
分に低下せず、圧延中にＡｒ3 点を下回ったり、製品板
の結晶粒径が著しく微細になったりすることがある。Ａ
ｒ3 点をより効果的に低下させるためには、冷却速度を
４０℃/s以上とすることが好ましい。冷却速度の上限は
操業の安定性や鋼板の加工性の観点から１００℃/s程度
までとするのがよい。The cooling rate at 880 ° C. or lower during finish hot rolling is preferably higher than 30 ° C./s. At 30 ° C / s or less, even if the C content and the B content are appropriate, the Ar 3 point does not decrease sufficiently, the Ar 3 point falls below the rolling point, or the crystal grain size of the product plate becomes extremely fine. It may become. A
In order to reduce the r 3 point more effectively, the cooling rate is preferably 40 ° C./s or more. The upper limit of the cooling rate is preferably about 100 ° C./s from the viewpoint of operation stability and workability of steel sheet.
【００３４】最終仕上げ圧延温度は、（Ａｒ3 点−２０
℃）以上とする。（Ａｒ3 点−２０℃）未満では、表層
に粗大粒が形成されて材質が劣化したり、加工時に肌荒
れが生じたり、また、操業が不安定になったりする。ま
た、材質（伸び、ｒ値等）の異方性も大きくなる。これ
らの観点で、Ａｒ3 点以上とするのがさらに望ましい。The final finishing rolling temperature is (Ar 3 points -20
℃) or higher. If it is less than (Ar 3 point−20 ° C.), coarse particles are formed in the surface layer and the material is deteriorated, the surface is roughened during processing, and the operation becomes unstable. Further, the anisotropy of the material (elongation, r value, etc.) also becomes large. From these viewpoints, it is more desirable that the number of Ar points is 3 or more.
【００３５】仕上げ熱延後の冷却速度は、特に限定する
ものではないが、材質上は、なるべく徐冷するのがよ
い。これは、冷却速度が速すぎると、粒成長が起き難
く、著しく微細な結晶粒になったり、一部だけが粒成長
して混粒組織となったりして、鋼板の加工性が劣悪なも
のとなる。The cooling rate after finish hot rolling is not particularly limited, but it is preferable to gradually cool the material as far as possible. This is because if the cooling rate is too fast, grain growth is difficult to occur, resulting in extremely fine crystal grains, or only a portion of the grains grows into a mixed grain structure, resulting in poor workability of the steel sheet. Becomes
【００３６】熱延後の巻取り温度も特に限定するもので
はない。しかし、時効性を確保するためには２５０℃以
上で巻取り、また、粒成長を促し、より優れた加工性を
確保するためには５５０℃以上で巻取るのがよい。さら
に、優れた深絞り性の必要な冷延鋼板用の素材として用
いる場合には、６５０℃以上で巻取ることが好ましい。The winding temperature after hot rolling is not particularly limited. However, in order to secure the aging property, it is preferable to wind it at 250 ° C. or higher, and to accelerate grain growth and to secure more excellent workability, it is preferable to wind it at 550 ° C. or higher. Further, when it is used as a material for a cold-rolled steel sheet that requires excellent deep drawability, it is preferably wound at 650 ° C or higher.
【００３７】調質圧延は目的に応じて行う。すなわち、
形状矯正や表面粗度の調整、さらには時効性の確保の観
点から圧下率０．５％以上の調質圧延を施すことが好ま
しい。なお、調質圧延は、仕上げ熱延後にインラインで
行ってもよいし、巻取り後や酸洗後にオフラインで行っ
てもよい。巻取り後には酸洗してもよい。The temper rolling is performed according to the purpose. That is,
From the viewpoint of correcting the shape, adjusting the surface roughness, and securing the aging property, it is preferable to perform temper rolling with a rolling reduction of 0.5% or more. The temper rolling may be performed inline after finish hot rolling, or offline after winding or pickling. You may pickle after winding.
【００３８】本発明による熱延鋼板は、巻取り後や酸洗
後あるいは調質圧延後にそのまま製品としてもよいし、
これに種々の表面処理を施してもよい。さらに、この熱
延鋼板を冷延素材として用いても構わない。例えば、缶
用の冷延素材として用いれば、異方性の小さい（耳高さ
の低い）冷延板を製造することができる。本発明におけ
る熱延鋼板は、延性、張出し成形性、穴拡げ性等の加工
性に優れ、かつ常温非時効性をも兼ね備えている。The hot rolled steel sheet according to the present invention may be directly used as a product after winding, pickling or temper rolling.
This may be subjected to various surface treatments. Further, the hot-rolled steel sheet may be used as a cold-rolled material. For example, when used as a cold-rolled material for cans, a cold-rolled sheet with small anisotropy (low ear height) can be manufactured. The hot-rolled steel sheet according to the present invention is excellent in workability such as ductility, stretch formability, and hole expandability, and also has non-aging at room temperature.
【００３９】[0039]
（実施例１）０．０５％Ｃ−０．２５％Ｍｎ−０．００
２５％Ｂを主成分とする鋼における７段からなる仕上げ
熱延を行う際に３段目および４段目相当の加工の合計の
圧下率とＡｒ3 点との関係について検討した結果が図２
である。仕上げ相当の加工熱処理は、図１に示す条件で
実験室的に行った。(Example 1) 0.05% C-0.25% Mn-0.00
Fig. 2 shows the results of an examination of the relationship between the total rolling reduction and the Ar 3 point in the third- and fourth-stage processing when performing hot rolling with 7 stages in steel containing 25% B as the main component.
It is. The thermo-mechanical treatment corresponding to finishing was performed in a laboratory under the conditions shown in FIG.
【００４０】すなわち、１２５０℃で加熱した後、９７
０〜８４０℃の温度でパス間時間を５〜０．５ｓとする
６段の加工を行った。加工を６段としたのは、７段の仕
上げ圧延を行う際に７段目入り側でＡｒ3 点を大きく下
回らないことが重要であるので、６段加工後のＡｒ3 点
を調査するためである。That is, after heating at 1250 ° C., 97
Six-step processing was performed at a temperature of 0 to 840 ° C. and an interpass time of 5 to 0.5 s. Processing to that six stages, so that not less than large Ar 3 point in the seventh stage entry side when performing finish rolling of 7-stage is important, in order to investigate the Ar 3 point after 6-stage process Is.
【００４１】なお、３段目および４段目の合計の圧下率
（Ｒ（％）とする）とは、３段目手前の板厚ｔ１（m
m）、４段直後の板厚ｔ２（mm）とすると、Ｒ（％）＝
（ｔ１−ｔ２）／ｔ１×１００または、（Ｘ−４）段目
の圧下率ｒ１（％）、（Ｘ−３）段目の圧下率ｒ２
（％）としたとき、Ｒ（％）＝｛１−（１−ｒ１／１０
０）（１−ｒ２／１００）｝×１００で定義される。図
２より明らかなとおり、このＲが６０％以上となるとＡ
ｒ3 点の低下に顕著な効果があることが明らかとなっ
た。The total reduction ratio of the third step and the fourth step (denoted as R (%)) means the plate thickness t1 (m
m) Assuming that the plate thickness t2 (mm) immediately after four steps, R (%) =
(T1-t2) / t1 × 100 or (X-4) -th stage reduction rate r1 (%), (X-3) -th stage reduction rate r2
(%), R (%) = {1- (1-r1 / 10
0) (1-r2 / 100)} × 100. As is clear from FIG. 2, when this R becomes 60% or more, A
It became clear that the reduction of r 3 point had a remarkable effect.
【００４２】（実施例２）表１に示す化学成分を有する
極低炭素鋼および低炭素鋼を真空溶解にて溶製し、熱間
圧延を施した。熱間圧延条件は、加熱温度１２１０℃、
７段からなる仕上げ熱延における３段目と４段目の圧下
率を合計で７５％、なお、３段目と４段目の圧延は、８
５０〜９４０℃の間で行った。５段目、６段目の圧下率
を合計で３０％とした。Example 2 Ultra-low carbon steel and low carbon steel having the chemical components shown in Table 1 were melted by vacuum melting and hot rolled. The hot rolling conditions are heating temperature 1210 ° C,
The rolling reduction of the 3rd and 4th stages in the finish hot rolling consisting of 7 stages is 75% in total, and the rolling of the 3rd and 4th stages is 8
It carried out between 50-940 degreeC. The total reduction rate of the 5th and 6th steps was 30%.
【００４３】仕上げ熱延中の８８０℃以下での平均冷却
速度は約３８℃/s、仕上げ圧延後から巻取りまでの平均
冷却速度は約１６℃/s、巻取り相当処理温度は６４０℃
である。なお、板厚は０．８〜１．４mmとし、仕上げ最
終圧延温度は７５０〜８２０℃とした。During the finish hot rolling, the average cooling rate at 880 ° C. or lower is about 38 ° C./s, the average cooling rate from finish rolling to winding is about 16 ° C./s, and the processing temperature equivalent to winding is 640 ° C.
It is. The plate thickness was 0.8 to 1.4 mm, and the final finishing rolling temperature was 750 to 820 ° C.
【００４４】巻取り後、酸洗し、圧下率１．０％の調質
圧延を施し、引張試験に供した。ここで、引張試験は、
ＪＩＳ５号試験片を用いて行った。Ａｒ3 点の測定は１
〜６段目の仕上げ圧延と同等の加工熱処理を施して、変
態による膨張量を測定することにより行った。After winding, it was pickled, temper-rolled with a rolling reduction of 1.0%, and subjected to a tensile test. Here, the tensile test is
It carried out using the JIS No. 5 test piece. 1 for Ar 3 point
It was performed by performing a thermomechanical treatment equivalent to the finishing rolling of the sixth stage and measuring the expansion amount due to the transformation.
【００４５】表２から明らかなように、本発明の成分を
有する鋼を適切な条件で熱延した場合には、優れた材質
を得られることが分かる。これに対して、比較例では、
Ａｒ3 点が充分に低下しないため、仕上げ温度がＡｒ3
点を大きく下回り、材質が劣悪なものになった。As is clear from Table 2, when the steel having the components of the present invention is hot-rolled under appropriate conditions, an excellent material can be obtained. On the other hand, in the comparative example,
Since the Ar 3 point does not decrease sufficiently, the finishing temperature is Ar 3
It was far below the point and the material was inferior.
【００４６】[0046]
【表１】 [Table 1]
【００４７】[0047]
【表２】 [Table 2]
【００４８】（実施例３）表３に示した鋼を実機にて出
鋼し、加熱温度１２１０℃、巻取り温度６００℃とする
実機熱間圧延を施した。７段からなる仕上げ圧延におけ
る各段入り側の温度および圧下率を種々変化させた。Example 3 The steels shown in Table 3 were tapped in an actual machine and subjected to actual hot rolling at a heating temperature of 1210 ° C. and a winding temperature of 600 ° C. The temperature and the rolling reduction on the entry side of each stage in the finish rolling consisting of 7 stages were variously changed.
【００４９】このとき仕上げ圧延中８８０℃以下での平
均冷却速度は約３５℃/s、仕上げ圧延後、巻取りまでの
平均冷却速度は約１５℃/sとした。巻取り後、酸洗し、
圧下率０．８％の調質圧延を施し、引張試験に供した。
ここで、引張試験は、ＪＩＳ５号試験片を用いて行っ
た。At this time, the average cooling rate during finish rolling at 880 ° C. or lower was about 35 ° C./s, and the average cooling rate after finish rolling and winding was about 15 ° C./s. After winding, pickling,
The sheet was subjected to temper rolling with a rolling reduction of 0.8% and subjected to a tensile test.
Here, the tensile test was performed using a JIS No. 5 test piece.
【００５０】表４から明らかなように、本発明の熱延条
件、すなわち、中段での大圧下、後段で軽圧下すること
により、優れた材質を得られることが分かる。これに対
して、比較例では、仕上げ温度を確保することができ
ず、したがって材質が著しく劣化した。As is clear from Table 4, excellent materials can be obtained by the hot rolling conditions of the present invention, ie, large reduction in the middle stage and light reduction in the latter stage. On the other hand, in the comparative example, the finishing temperature could not be secured, and therefore the material was significantly deteriorated.
【００５１】[0051]
【表３】 [Table 3]
【００５２】[0052]
【表４】 [Table 4]
【００５３】[0053]
【表５】 [Table 5]
【００５４】[0054]
【表６】 [Table 6]
【００５５】[0055]
【表７】 [Table 7]
【００５６】（実施例４）実施例３の表３に示した成分
を有するスラブを実験室熱間圧延に供した。加熱温度１
２６０℃とし、粗圧延終了後、１０５０℃に到達と同時
に曲率１ｍの曲げ加工を行い、１０５０℃の保熱炉に装
入し、９０秒間保持し、炉より取り出した後曲げ戻し、
６段の仕上げ熱延を行った。２段目は、入り側温度９２
０℃、圧延率５０％、３段目は温度９１０℃、圧下率４
０％、４段および５段の合計の圧下率は３２％とした。Example 4 A slab having the components shown in Table 3 of Example 3 was subjected to laboratory hot rolling. Heating temperature 1
After the rough rolling is completed, the temperature is set to 260 ° C., and after the rough rolling is reached, bending is performed with a curvature of 1 m at the same time.
Six stages of finish hot rolling were performed. The second stage has an inlet temperature of 92.
0 ° C, rolling rate 50%, third stage temperature 910 ° C, rolling reduction 4
The total reduction rate of 0%, 4th stage and 5th stage was 32%.
【００５７】また、仕上げ圧延では、粗バーの末端部を
先行材および後続材に接合して連続的に仕上げる熱延も
行った。また、比較として粗圧延後に曲げ、保熱炉での
保持、巻戻しを行わず、かつ先行材、後続材との接合も
行わない単独での熱延も行った。仕上げ熱延中の８８０
℃以下での冷却速度は４１〜４５℃とした。Further, in the finish rolling, hot rolling was carried out in which the end portion of the rough bar was joined to the preceding material and the succeeding material to continuously finish. In addition, as a comparison, hot rolling alone was performed without bending after rough rolling, holding in a heat retention furnace, rewinding, and joining with the preceding and succeeding materials. 880 during finishing hot rolling
The cooling rate below ℃ was 41 to 45 ℃.
【００５８】仕上げ温度は種々変化させ、仕上げ後の平
均冷却速度は、約１２℃/s（放冷）とした。調質圧延の
圧下率は、１．２％とし、板厚は１．２mmとした。巻取
り温度は、５８０℃とした。The finishing temperature was variously changed, and the average cooling rate after finishing was about 12 ° C./s (cooling). The reduction ratio of temper rolling was 1.2%, and the plate thickness was 1.2 mm. The winding temperature was 580 ° C.
【００５９】なお、仕上げを連続的に行った際の仕上げ
最先端および最末端部相当位置（表５）とは、先行材、
後続材との接合を行って仕上げた熱延鋼板の長手方向に
おいて、接合を行わずに圧延したときの最先端、最末端
に相当する位置のことである。すなわち、接合部に近い
位置に相当する。ただし、接合時の熱影響部からは離れ
た場所の材質を評価した。Incidentally, the positions corresponding to the leading edge of the finish and the position corresponding to the endmost portion (Table 5) when the finish is continuously carried out are the preceding material,
In the longitudinal direction of the hot-rolled steel sheet finished by joining with the succeeding material, it is the position corresponding to the leading edge and the extreme end when rolled without joining. That is, it corresponds to a position near the joint. However, the material of the place apart from the heat affected zone at the time of joining was evaluated.
【００６０】表５から明らかなように、粗圧延と仕上げ
圧延の間に所定の条件内で曲げ加工と保持を行うこと
で、材質がさらに向上することが分かる。さらに、連続
的に仕上げ熱延を施すとより一層、長手方向に均一でか
つ優れた延性が得られることが分かる。As is clear from Table 5, the material is further improved by performing bending and holding within a predetermined condition between rough rolling and finish rolling. Further, it can be seen that when the finish hot rolling is continuously performed, more uniform and excellent ductility can be obtained in the longitudinal direction.
【００６１】[0061]
【表８】 [Table 8]
【００６２】[0062]
【発明の効果】本発明によれば、Ａｒ3 点を効果的に低
下させることによって、加工性に優れた熱延鋼板を低コ
ストで安定して得ることができ、冷延鋼板の代替として
使用することも可能である。According to the present invention, by effectively reducing the Ar 3 point, a hot rolled steel sheet excellent in workability can be stably obtained at low cost, and is used as a substitute for the cold rolled steel sheet. It is also possible to do so.
【図１】仕上げ３，４段の合計圧下率がＡｒ3 点に及ぼ
す影響を検討するための加工熱処理履歴を表す。FIG. 1 shows a history of thermo-mechanical treatment for studying the effect of the total reduction ratio of finishing 3 and 4 steps on the Ar 3 point.
【図２】仕上げ３，４段の合計圧下率とＡｒ3 点との関
係の図表を表す。FIG. 2 is a diagram showing a relationship between a total reduction ratio of finishing 3 and 4 steps and an Ar 3 point.
フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２２Ｃ 38/14 Ｃ２２Ｃ 38/14 (72)発明者 橋本 夏子 富津市新富20−１ 新日本製鐵株式会社技 術開発本部内 (72)発明者 土師 純治 大分市大字西ノ洲１番地 新日本製鐵株式 会社大分製鐵所内Continuation of front page (51) Int.Cl. 6 Identification number Internal reference number FI Technical indication C22C 38/14 C22C 38/14 (72) Inventor Natsuko Hashimoto 20-1 Shintomi, Futtsu-shi Nippon Steel Corporation Technical Development Headquarters (72) Inventor Junji Haji 1 Nishinosu, Oita-shi, Oita-shi Nippon Steel Corporation Oita Works
Claims (4)
し、 残部は鉄および不可避的不純物よりなるスラブの熱間圧
延に際し、Ｘ段からなる仕上げ熱延機の（Ｘ−４）段目
および（Ｘ−３）段目の圧延を、８４０℃以上９４０℃
未満の温度範囲で、かつそこでの圧下率で合計で６０％
以上とし、（Ｘ−２）と（Ｘ−１）段目の圧下率を合計
で４５％以下とし、最終仕上げ圧延温度を（Ａｒ3 点−
２０℃）以上とすることを特徴とする加工性に優れた熱
延鋼板の製造方法。1. By weight%, C = 0.01 to 0.15%, Mn = 0.03 to 2.0%, Si ≦ 0.5%, Al = 0.003 to 0.2%, P ≤0.10%, S ≤0.02%, N ≤0.007%, B ≤0.0015 to 0.01%, with the balance being iron and unavoidable impurities. During the hot rolling, the rolling of the (X-4) th stage and the (X-3) th stage of the finishing hot rolling machine including the X stage is performed at 840 ° C or more and 940 ° C or more.
60% in total in the temperature range below
In the above, the total reduction ratio of the (X-2) and (X-1) th stages is 45% or less, and the final finishing rolling temperature is (Ar 3 point-
20 ° C.) or higher, and a method for manufacturing a hot-rolled steel sheet having excellent workability, which is characterized in that
０．０５％、Ｎｂ＝０．００３〜０．０５％のうち１種
または２種を含有することを特徴とする請求項１記載の
加工性に優れた熱延鋼板の製造方法。2. Further, in weight%, Ti = 0.003 to.
The method for producing a hot-rolled steel sheet having excellent workability according to claim 1, wherein the hot-rolled steel sheet contains one or two of 0.05% and Nb = 0.003 to 0.05%.
後、巻戻し、巻終わり端より連続的に仕上げ熱延を行う
ことを特徴とする請求項１または２記載の加工性に優れ
た熱延鋼板の製造方法。3. An excellent workability according to claim 1 or 2, characterized in that after the rough rolled rough bar is wound into a coil shape, it is rewound and finish hot rolling is continuously performed from the winding end end. Method for producing hot rolled steel sheet.
後、巻戻し、その巻終わり端と先行する粗バーの末端と
を接合し、連続的に仕上げ熱延を行うことを特徴とする
請求項１または２記載の加工性に優れた熱延鋼板の製造
方法。4. A method of winding a rough-rolled rough bar into a coil, unwinding it, joining the end of winding and the end of the preceding rough bar, and continuously performing finish hot rolling. The method for producing a hot-rolled steel sheet having excellent workability according to claim 1 or 2.
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|---|---|---|---|
| JP20622995A JP3793253B2 (en) | 1995-08-11 | 1995-08-11 | Manufacturing method of hot-rolled steel sheet with excellent workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20622995A JP3793253B2 (en) | 1995-08-11 | 1995-08-11 | Manufacturing method of hot-rolled steel sheet with excellent workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0953123A true JPH0953123A (en) | 1997-02-25 |
| JP3793253B2 JP3793253B2 (en) | 2006-07-05 |
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ID=16519907
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| JP20622995A Expired - Fee Related JP3793253B2 (en) | 1995-08-11 | 1995-08-11 | Manufacturing method of hot-rolled steel sheet with excellent workability |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009501635A (en) * | 2005-07-19 | 2009-01-22 | アルベディ，ジョバンニ | Production method and plant for steel sheet without interruption |
| WO2013105395A1 (en) * | 2012-01-12 | 2013-07-18 | 新日鐵住金株式会社 | Low alloy steel |
| JP2016529394A (en) * | 2013-07-03 | 2016-09-23 | ポスコ | Hot-rolled steel sheet with excellent workability and aging resistance and method for producing the same |
| WO2020261965A1 (en) * | 2019-06-24 | 2020-12-30 | Ｊｆｅスチール株式会社 | Steel sheet for can, and method for manufacturing same |
-
1995
- 1995-08-11 JP JP20622995A patent/JP3793253B2/en not_active Expired - Fee Related
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009501635A (en) * | 2005-07-19 | 2009-01-22 | アルベディ，ジョバンニ | Production method and plant for steel sheet without interruption |
| WO2013105395A1 (en) * | 2012-01-12 | 2013-07-18 | 新日鐵住金株式会社 | Low alloy steel |
| JP5418702B2 (en) * | 2012-01-12 | 2014-02-19 | 新日鐵住金株式会社 | Low alloy steel |
| CN104053803A (en) * | 2012-01-12 | 2014-09-17 | 新日铁住金株式会社 | Low alloy steel |
| AU2012365128B2 (en) * | 2012-01-12 | 2015-09-03 | Nippon Steel Corporation | Low alloy steel |
| JP2016529394A (en) * | 2013-07-03 | 2016-09-23 | ポスコ | Hot-rolled steel sheet with excellent workability and aging resistance and method for producing the same |
| WO2020261965A1 (en) * | 2019-06-24 | 2020-12-30 | Ｊｆｅスチール株式会社 | Steel sheet for can, and method for manufacturing same |
| JP6881696B1 (en) * | 2019-06-24 | 2021-06-02 | Ｊｆｅスチール株式会社 | Steel sheet for cans and its manufacturing method |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3793253B2 (en) | 2006-07-05 |
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