JPS62270726A - Manufacture of cold rolled steel sheet having superior workability - Google Patents
Manufacture of cold rolled steel sheet having superior workabilityInfo
- Publication number
- JPS62270726A JPS62270726A JP9005386A JP9005386A JPS62270726A JP S62270726 A JPS62270726 A JP S62270726A JP 9005386 A JP9005386 A JP 9005386A JP 9005386 A JP9005386 A JP 9005386A JP S62270726 A JPS62270726 A JP S62270726A
- Authority
- JP
- Japan
- Prior art keywords
- slab
- cold
- hot rolling
- steel sheet
- rolling
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 22
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 238000005098 hot rolling Methods 0.000 claims abstract description 29
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 25
- 239000010959 steel Substances 0.000 claims abstract description 25
- 238000007711 solidification Methods 0.000 claims abstract description 12
- 230000008023 solidification Effects 0.000 claims abstract description 12
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 238000000137 annealing Methods 0.000 claims description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 238000005097 cold rolling Methods 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 238000005336 cracking Methods 0.000 abstract description 15
- 238000005096 rolling process Methods 0.000 abstract description 11
- 239000000203 mixture Substances 0.000 abstract description 3
- 238000005266 casting Methods 0.000 abstract 1
- 238000000034 method Methods 0.000 description 16
- 239000000463 material Substances 0.000 description 6
- 230000032683 aging Effects 0.000 description 5
- 230000003679 aging effect Effects 0.000 description 4
- 238000001816 cooling Methods 0.000 description 4
- 238000009749 continuous casting Methods 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 230000002596 correlated effect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 229910000655 Killed steel Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000001186 cumulative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 230000002269 spontaneous effect Effects 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
３、発明の詳細な説明
〔産業上の利用分野〕
本発明は加工性の優れた冷延鋼板の製造法に関するもの
である。[Detailed Description of the Invention] 3. Detailed Description of the Invention [Field of Industrial Application] The present invention relates to a method for manufacturing a cold-rolled steel sheet with excellent workability.
加工性の優れた冷延鋼板は、従来限定された鋼成分の鋼
を２００〜２５０ｍ厚みの連続鋳造スラブまたは分塊ス
ラブとし、これを２〜６１１Ｉ厚みまで圧延し、酸洗・
冷間圧延・焼鈍工程を経て製造されている。この場合、
熱間圧延を２００〜２５０１厚より２〜６１■厚まで圧
延するため、強大な圧延工場を必要とし、その消費エネ
ルギーも多大なものとなる。最近、上記の欠点を克服す
る方法として、鋳片厚みを成品厚みにできるだけ近づけ
ようという試みがなされつつある。具体的な方法として
、熱間圧延を行なわないで、直接冷延素材を連続鋳造に
より製造するものと、熱間圧延工程の中間厚みの鋳片を
製造し、熱間圧延を簡略化するものが考えられている。Cold-rolled steel sheets with excellent workability are made by converting steel with conventionally limited steel components into continuous casting slabs or blooming slabs with a thickness of 200 to 250 m, rolling them to a thickness of 2 to 611 I, pickling and processing.
Manufactured through cold rolling and annealing processes. in this case,
Since hot rolling is performed from 200 to 2501 mm thick to 2 to 61 mm thick, a powerful rolling mill is required, and its energy consumption is also large. Recently, attempts have been made to make the slab thickness as close as possible to the finished product thickness as a way to overcome the above-mentioned drawbacks. Specifically, there are two methods: one is to directly produce a cold-rolled material by continuous casting without hot rolling, and the other is to produce slabs with an intermediate thickness during the hot rolling process to simplify the hot rolling process. It is considered.
前者の方法で製造された冷延鋼板は硬質で加工性が劣っ
ており、加えて、加工時に肌あれが発生し、加工用とし
て用いられない。一方後者の方法で製造された場合は、
加工時の肌あれこそないが、やはり硬質で加工性が劣る
。加えて凝固後の鋳片を直接熱間圧延する場合は圧延時
に鋼板に割れが発生するという欠点が生じる。Cold-rolled steel sheets manufactured by the former method are hard and have poor workability, and in addition, roughness occurs during processing, so they cannot be used for processing. On the other hand, if manufactured by the latter method,
There is no rough skin during processing, but it is still hard and has poor workability. In addition, when the slab after solidification is directly hot rolled, there is a drawback that cracks occur in the steel plate during rolling.
この発明は、前述の従来技術における問題点を゛解決し
た、加工性にすぐれた冷延鋼板の製造方法を提供するこ
とを目的としてなされた。The present invention has been made with the object of providing a method for manufacturing a cold-rolled steel sheet with excellent workability, which solves the problems in the prior art described above.
本発明者等は、鋳片厚み、凝固後の熱履歴を種種検討し
た結果、鋼成分を限定し、凝固後の熱履歴のコントロー
ルにより熱延での粗圧延工程の省略が可能で熱延時の割
れがなく、しかも加工性の優れた冷延鋼板を製造できる
ことを知見し、本発明を完成した。As a result of examining various slab thicknesses and thermal history after solidification, the present inventors have determined that by limiting the steel composition and controlling the thermal history after solidification, it is possible to omit the rough rolling process during hot rolling. The present invention was completed based on the discovery that it is possible to produce a cold-rolled steel sheet that is free from cracks and has excellent workability.
本発明の要旨とするところは、重量％でＣ：０、０７０
％以下、Ｍｎ ： ０．０５〜０．５０％、Ｓ：０．０
１５％以下、ＡＪ！：０．００５〜０．１００％、及び
必要に応じてＢを０．３≦Ｂ／Ｎ≦１．５の範囲で含存
し残部が鉄および不可避的不純物からなる溶鋼を２０〜
８０ｍｍ厚の鋳片とし、この凝固直後の鋳片を熱間圧延
するに際し、１１００〜９５０℃の温度域に３分〜６０
分間滞在せしめた後に熱間圧延し、引続いて、冷間圧延
、焼鈍することを特徴とする加工性の優れた冷延鋼板の
製造法にある。The gist of the present invention is that C:0.070 in weight%
% or less, Mn: 0.05-0.50%, S: 0.0
Less than 15%, AJ! : 0.005 to 0.100%, and if necessary, molten steel containing B in the range of 0.3≦B/N≦1.5, with the balance consisting of iron and inevitable impurities.
When hot rolling the slab immediately after solidification, the slab is 80 mm thick.
The present invention provides a method for producing a cold-rolled steel sheet with excellent workability, which is characterized by hot rolling after being held for a minute, followed by cold rolling and annealing.
まず、本発明の加工用冷延鋼板の成分限定について説明
する。First, the component limitations of the cold-rolled steel sheet for processing of the present invention will be explained.
Ｃは添加量が多くなると硬質となり、加工性を劣化せし
める元素であることが良く知られており、Ｃ！ｔが０．
０７０％以上になると、本発明の方法でも加工性が劣化
するので、上限を０．０７０％とした。好ましい範囲は
０．０５％以下である。Ｃ９が低ければ、低いほど、加
工性が良好となるので、ｃｌの下限は工業的に実施可能
な０．００１０％とした。It is well known that C becomes hard and deteriorates workability when added in a large amount, and C! t is 0.
If it exceeds 0.070%, the processability deteriorates even with the method of the present invention, so the upper limit was set at 0.070%. The preferred range is 0.05% or less. The lower the C9, the better the processability, so the lower limit of cl was set at 0.0010%, which is industrially practicable.
Ｍｎは熱間加工時のＳに誘起される熱間脆性を、防止す
るため、本発明の方法でも０．０７％以上必要である。Mn is required to be 0.07% or more in the method of the present invention in order to prevent hot embrittlement induced by S during hot working.
Ｍｎ量が０．５０％を超えると、加工性を劣化せしめ、
本発明の特徴を損う。したがってＭｎ量は０．０７〜０
．５０％に限定した。好ましい範囲は０．１０〜０．３
０％である。When the amount of Mn exceeds 0.50%, processability deteriorates,
This would detract from the features of the invention. Therefore, the amount of Mn is 0.07~0
．． Limited to 50%. The preferred range is 0.10-0.3
It is 0%.
Ｓは熱間加工時の割れを誘発する元素であるため１、低
い方が好ましい。Ｓは本発明では、加工性に大きな影響
を与える成分である。Ｓｉが０，０１５゜％を超えると
鋼が硬質化し、加工性が劣化する。Since S is an element that induces cracking during hot working, a lower value is preferable. In the present invention, S is a component that greatly affects processability. If Si exceeds 0.015%, the steel becomes hard and workability deteriorates.
好ましい範囲は０．０１０、％以下である。ｓｌの下限
は加工性の点から低い方が好ましいが、工業的に達成可
能な０．０００５％とする。The preferred range is 0.010% or less. Although the lower limit of sl is preferably lower from the viewpoint of processability, it is set to 0.0005%, which is industrially achievable.
Ａ、ｌはキルド鋼とするため、少な（とも０．００５％
必要である。一方Ａｌ量が０．１−．００％を超えると
鋼板が硬質化すると同時に鋼板の表面疵が増加し、しか
もコストの上昇をもたらす。したがってＡｌ量は０．０
０５〜０．１００％に限定した。好ましい範囲は０．０
１０〜ｏ、 ｏ ｓ ｏ％である。A and l are killed steel, so they are small (both 0.005%
is necessary. On the other hand, the amount of Al is 0.1-. If it exceeds 00%, the steel plate becomes hard and at the same time the surface flaws of the steel plate increase, and furthermore, the cost increases. Therefore, the amount of Al is 0.0
It was limited to 0.05 to 0.100%. The preferred range is 0.0
10~o, oso%.
以上本発明の基本成分の限定理由について述べた。この
基本成分に窒化物形成元素であるＢを添加することによ
って、本発明の特徴がさらに発揮される。Ｂを添加する
場合は０．３≦Ｂ／Ｎ≦土５の範囲である。Ｂ／Ｎが０
．３未満ではＢ添加による加工性向上効果がなく、Ｂ／
Ｎが１６．５を超えると逆に加工性が低下する。The reasons for limiting the basic components of the present invention have been described above. By adding B, which is a nitride-forming element, to this basic component, the features of the present invention are further exhibited. When B is added, the range is 0.3≦B/N≦Soil5. B/N is 0
．． If it is less than 3, there is no effect of improving workability by adding B, and
When N exceeds 16.5, workability deteriorates.
その他のＰ、Ｓｉ、Ｏ等の不純物元素は特に限定しない
が、できるかぎり少ないことが鋼板の加工性を良好とす
る点７！りら好ましい。Other impurity elements such as P, Si, and O are not particularly limited, but keeping them as small as possible improves the workability of the steel sheet.7! Rira is preferable.
次に上記の如き限定成分の加工性の優れた冷延鋼板の製
造方法について説明する。Next, a method for manufacturing a cold-rolled steel sheet with excellent workability using the above-mentioned limiting components will be explained.
実験室で：ｃ：ｏ、ｏ３％、Ｍｎ：０．２０％、Ｓ：０
．００６％、Ａ１：０．０４０％、Ｎ ： ０．００２
１％、Ｐ：０．００８％、Ｓｉ：０．０１０％の溶鋼を
４Ｑｍｍ厚みの鋳片とし、その鋳片の凝固後の冷速。In the laboratory: c: o, o3%, Mn: 0.20%, S: 0
．． 006%, A1: 0.040%, N: 0.002
1%, P: 0.008%, Si: 0.010% molten steel is made into a slab with a thickness of 4Qmm, and the cooling rate after solidification of the slab.
冷却パターンを種々に変え、続いて熱間圧延により３．
７１ｍの熱延鋼板とした。これを脱スケール後に０．８
０ ｍｍまで冷間圧延し、７２５℃×１分＋３５０”Ｃ
，Ｘ３分の焼鈍を行い、１．０％の調質圧延後に材質特
性を調査した。また熱延板の耳割れ発生程度も冷間圧延
前に調査した。3. Various cooling patterns followed by hot rolling.
A 71 m hot rolled steel plate was used. After descaling this, 0.8
Cold rolled to 0 mm, 725℃ x 1 minute + 350"C
, X3 minutes, and the material properties were investigated after 1.0% temper rolling. The degree of edge cracking in the hot rolled sheets was also investigated before cold rolling.
第１図は鋳片の圧延開始までの熱履歴において５０℃間
隔でその温度域で５分以上の滞在時間のある温度域（５
分以上の滞在時間を有するすべての温度域を含む）と冷
延鋼板の伸びの関係を示した。第１図より判るように、
１１５０〜９５０℃温度域に５分以上滞在せしめた後に
熱間圧延したものは伸びが優れていることが判る。１１
５０℃超のあるいは９５０℃未満の温度域で５分以上の
滞在時間を有する熱履歴のものは、伸びのバラツキが大
きい。そこで１１５０〜９５０℃間の５０℃間隔の温度
域で５分以上滞在する熱履歴材はこの温度域にプロット
し、それ以外の温度域からは除いた結果を同図の点線で
示した。この図は１１５０〜９５０℃の温度範囲での滞
在時間が重要であることが判る。そこで同実験から１１
５０〜９５０℃の温度範囲における熱延開始までの滞在
時間と冷延鋼板の伸び、ｆ値の関係を第２図に示した。Figure 1 shows the thermal history of the slab up to the start of rolling, at 50°C intervals, where the residence time is 5 minutes or more (50°C).
(including all temperature ranges with a residence time of 1 minute or more) and the elongation of cold-rolled steel sheets. As can be seen from Figure 1,
It can be seen that those which were hot rolled after staying in the temperature range of 1150 to 950°C for 5 minutes or more had excellent elongation. 11
Those with a thermal history of 5 minutes or more in a temperature range of more than 50°C or less than 950°C have large variations in elongation. Therefore, thermal history materials that stay in a temperature range of 1150 to 950°C at intervals of 50°C for 5 minutes or more are plotted in this temperature range, and the results excluding other temperature ranges are shown by the dotted line in the figure. This figure shows that the residence time in the temperature range of 1150 to 950°C is important. Therefore, from the same experiment, 11
FIG. 2 shows the relationship between the residence time until the start of hot rolling, elongation of the cold rolled steel sheet, and f value in the temperature range of 50 to 950°C.
同様に時効指数と１１５０〜９５０℃の温度範囲での滞
在時間の関係を第３図に示した。第２図よりｆ値、伸び
の加工性と相関のある特性は、１１５０〜９５０℃の温
度範囲で３分以上の滞在時間で良好となることが判る。Similarly, FIG. 3 shows the relationship between the aging index and the residence time in the temperature range of 1150 to 950°C. From FIG. 2, it can be seen that the properties correlated with workability, such as f value and elongation, become good when the residence time is 3 minutes or more in the temperature range of 1150 to 950°C.
一方、時効指数は１１５０〜９５０℃の温度範囲での滞
在時間が６０分以上になると大きくなり、鋼板の時効性
が劣化することが判る。On the other hand, the aging index increases when the residence time in the temperature range of 1150 to 950° C. exceeds 60 minutes, indicating that the aging properties of the steel sheet deteriorate.
第４図は熱延板での耳割れ程度と１１００〜９５０℃で
の滞在時間の関係を示した。割れの評点は１が割れなし
、２は割れが若干認められる、３は割れ発生の３段階で
評価した。第４図より１１００〜９５０℃の滞在時間が
３分以内で割れが発生しており、３分以上を経て、圧延
したものは割れが殆どない事がわかる。FIG. 4 shows the relationship between the degree of edge cracking in a hot rolled sheet and the residence time at 1100 to 950°C. The cracking was evaluated on a three-level scale, with 1 being no cracking, 2 being slightly cracked, and 3 being cracking. From FIG. 4, it can be seen that cracks occur within 3 minutes of residence time at 1100 to 950°C, and that there are almost no cracks in the rolled products after 3 minutes or more.
以上の実験事実に基づいて、凝固後の鋳片を熱間圧延す
るに際し、１１５０〜９５０°Ｃの温度域に３分〜６０
分滞在せしめた後に熱間圧延する条件を、加工性が優れ
、時効性が優れ、しかも熱延板での割れが発生しないも
のとして限定した。この温度域での滞在時間を５分以上
とすることによって安定して本発明の目的が達成される
。Based on the above experimental facts, when hot rolling a slab after solidification, it is necessary to heat it in a temperature range of 1150 to 950°C for 3 minutes to 60°C.
The conditions for hot rolling after staying for a minute were limited to those that provide excellent workability, excellent aging properties, and do not cause cracking in the hot rolled sheet. By setting the residence time in this temperature range to 5 minutes or more, the object of the present invention can be stably achieved.
第５図に鋳片厚みと冷延鋼板のｆ値の関係を示す。鋳片
厚み以外の条件は以下のとおりである。FIG. 5 shows the relationship between slab thickness and f-value of cold-rolled steel sheets. Conditions other than slab thickness are as follows.
Ｃ：０．０２５％、Ｍｎ：０．２０％、Ａ ｔｔ ：
０．０３６％、Ｓ ： ０．００５％、Ｎ ： ０．０
０２０％、の溶鋼より鋳片を製造し、鋳片の熱履歴とし
ては１１００〜９５０℃での滞在時間を１５分とし、３
．７龍厚みまで熱延し、脱スケール後、０．８０鶴まで
の冷延、７５０℃×１分＋３５０℃×３分の焼鈍、１．
５％のスキンパス圧延を行った。第５図より判るように
２０鶴未満の鋳片厚みでは〒値が低い。この事実に基づ
いて鋳片の下限厚みを限定した。好ましい範囲は３０ｉ
ｎ以上である。鋳片の厚みの上限は本発明の目的である
、熱延設備の簡略、熱延消費エネルギーの低減という観
点から、最大 ８０１ｍまでである。C: 0.025%, Mn: 0.20%, Att:
0.036%, S: 0.005%, N: 0.0
A slab was produced from molten steel of 0.020%, and the thermal history of the slab was 15 minutes at 1100 to 950°C.
．． Hot rolled to a thickness of 7. After descaling, cold rolled to a thickness of 0.80 mm, annealed at 750°C x 1 minute + 350°C x 3 minutes, 1.
5% skin pass rolling was performed. As can be seen from Fig. 5, the 〒 value is low when the slab thickness is less than 20 mm. Based on this fact, the minimum thickness of the slab was determined. The preferred range is 30i
It is greater than or equal to n. The upper limit of the thickness of the slab is up to 801 m from the viewpoint of simplifying hot rolling equipment and reducing hot rolling energy consumption, which are the objectives of the present invention.
熱延仕上温度は通常工程と同様に、Ａｒ１点以上で行う
ことが好ましい。熱延後、通常行なわれる場合と同様、
制御冷却し、連続焼鈍材は６００〜７８０℃で、箱焼鈍
材は５００〜７１０℃の温度で捲取ることが好ましい。The hot rolling finishing temperature is preferably carried out at an Ar point or higher, similar to the normal process. After hot rolling, as usual,
Controlled cooling is preferably carried out, and continuous annealing material is preferably rolled at a temperature of 600 to 780°C, and box annealing material is rolled at a temperature of 500 to 710°C.
熱延板は脱スケール後に６０〜９０％の冷延を行う。焼
鈍は連続焼鈍でも、箱焼鈍でも本発明の特徴を発渾する
。焼鈍板は必要に応じ、調質圧延を行い、成品に供され
る。The hot rolled sheet is cold rolled by 60 to 90% after descaling. Both continuous annealing and box annealing exhibit the features of the present invention. The annealed plate is subjected to skin pass rolling as required, and then used as a finished product.
本発明の方法で製造された鋼板を表面処理鋼板として用
いても本発明の特徴を損なわない。Even if the steel sheet manufactured by the method of the present invention is used as a surface-treated steel sheet, the characteristics of the present invention will not be impaired.
第１表に示す成分および製造条件で冷延鋼板を製造し、
その材質特性および、熱延板での耳割れ程度を評価し、
同表に示した。熱延板の耳割れ評価は評点（１）割れな
し、（２）若干の割れあり、（３）割れ大の三段階で評
価した。A cold-rolled steel sheet is manufactured using the ingredients and manufacturing conditions shown in Table 1,
Evaluate the material properties and the degree of edge cracking in hot rolled sheets,
Shown in the same table. The edge cracking of the hot-rolled sheet was evaluated in three grades: (1) No cracking, (2) Slight cracking, and (3) Severe cracking.
第１表の結果から、本発明の方法で製造したものは、本
発明以外の方法で製造されたものより、高い延゛性、高
いＴ値、を示し、時効性も優れていることがわかる。加
えて、熱延板での耳割れも発生していない。From the results in Table 1, it can be seen that the products produced by the method of the present invention exhibit higher ductility, higher T value, and superior aging properties than those produced by methods other than the present invention. . In addition, no edge cracking occurred in the hot-rolled sheet.
コイル！１ｈｌｏ、１１，１２．１３は成分的に本発明
範囲外のものであるがいずれも加工性と相関のある伸び
、ｆ値が低い。コイルＦｌｈ１４は鋳片厚みが１５１＠
と本発明範囲外、コイル患１５は熱延開始までの１１５
０℃〜９５０℃温度範囲での滞在特開が本発明範囲外で
製造されたものであり、いずれも加工性が劣っている。coil! Although 1hlo, 11, and 12.13 are outside the scope of the present invention in terms of their components, they all have low elongation and f-value, which are correlated with workability. Coil Flh14 has a slab thickness of 151@
Out of the scope of the present invention, coil failure 15 is 115 until the start of hot rolling.
The JP-A patents with a temperature range of 0°C to 950°C were manufactured outside the range of the present invention, and both have poor processability.
コイル！ｌ＆ｌ１６は、１１５０〜９５０℃の滞在時間
が長すぎた場合であり、Ｔ値が優れているが、時効指数
が大きくなり、時効性がある。coil! l&l16 is a case where the residence time at 1150 to 950°C is too long, and the T value is excellent, but the aging index becomes large and there is aging property.
本発明に従えば、上記実施例からも明らかなように、限
定成分の鋼を連続鋳造して薄鋳片とし、鋳片の冷却過程
のコントロールにより、従来工程の如く、強力な熱間圧
延機列による累積大圧下の熱間圧延を行なわなくとも、
加工性が優れ、しかも時効性も良好な冷延鋼板が製造可
能となる。かくして工程の省力化にともなう、省エネル
ギー。According to the present invention, as is clear from the above embodiments, steel with a limited composition is continuously cast into thin slabs, and by controlling the cooling process of the slabs, a powerful hot rolling machine can be used as in the conventional process. Even without hot rolling with a large cumulative reduction in rows,
It becomes possible to produce a cold-rolled steel sheet with excellent workability and good aging resistance. In this way, energy is saved due to labor saving in the process.
コストの大幅な低減を可能とするから、本発明は産業上
著しく有用な発明である。The present invention is an industrially extremely useful invention because it enables a significant reduction in costs.
【図面の簡単な説明】
第１図は鋳片の圧延開始までの熱履歴において５０℃間
隔でその温度域で５分以上滞在時間のある温度域と冷延
鋼板の伸びの関係を示す図、第２図は鋳片の熱間圧延開
始までの１１５０〜９５０℃での滞在時間とｆ、Ｅｌの
関係を示す図、第３図は鋳片の熱間圧延開始までの１１
５０〜９５０℃での滞在時間と時効指数の関係を示す図
、第４図は鋳片の熱間圧延開始までの１１５０〜９５０
℃での滞在時間と熱延板の耳割れの関係を示す図、第５
図は鋳片厚みと冷延鋼板のｆ値の関係を示す図である。
特許出願人 新日本製鐵株式會社
温度域（０Ｃ）
／／θａ ′Ｃ−会４υて′の李ノ笠テ号；司りなり第
３図
／乙タクと〜ｑｓｏ’２７でヅｉＷＡ時１町傍）第５図
θ ２０ ＃ ｕ Ｊ
房鱒凡４与（ｍ晟）
手続補正書 （自発）
昭和６２年６月１０日
特許庁長官 黒 １）明 雄 殿
１、事件の表示
昭和６１年特許願第９００５３号
２、発明の名称
加工性の優れた冷延鋼板の製造法
３、補正をする者
事件との関係 特許出願人
東京都千代田区大手町二丁目６番３号
（６６５）新日本製鐵株式會社
代表者 武 １） 豊
４、代理人〒１００
東京都千代田区丸の内二丁目４番１号
６、補正の対象
明細書の特許請求の範囲の欄及び発明の詳細な説明の欄
７、補正の内容 、〈−−−へ／、；
−、、、。
（１）特許請求の範囲を別紙のとおり補正する。
（２）明細書３頁最下行ｒ Ｍｎ ： ０．０５〜０．
５０％」を「Ｍｎ ： ０．０７〜０．５０％」に補正
する。
（３）同１２頁第１表を別紙のとおり補正する。
特許請求の範囲
（１１重量％でＣ：０．０７０％以下、Ｍｎ：０．０７
〜０．５０％、Ｓ ： ０．０１５％以下、Ａ ｎ ：
０．００５〜０、１００％、残部が鉄および不可避的
不純物からなるン容鋼を２０〜８０龍厚の鋳片とし、こ
の凝固直後の鋳片を熱間圧延するに際し、１１５０〜９
５０℃の温度域に３分〜６０分滞在せしめた後に熱間圧
延し、引続いて冷間圧延、焼鈍することを特徴とする加
工性の優れた冷延鋼板の製造法。
（２） 重量％でＣ： ０．０７０％以下、Ｍｎ：０
．０７〜０．５０％、Ｓ ： ０．０１５％以下、Ａ
ｌ ７０．００５〜０、１００％に加えて、Ｂを０．３
≦Ｂ／Ｎ≦１．５の範囲で含有し、残部が鉄および不可
避的不純物からなる溶鋼を２０〜８０ｎ厚の鋳片とし、
この凝固直後の鋳片を熱間圧延するに際し、１１５０〜
９５０℃の温度域に３分〜６０分滞在せしめた後に熱間
圧延し、引続いて、冷間圧延、焼鈍することを特徴とす
る加工性の優れた冷延鋼板の製造法。[Brief explanation of the drawings] Figure 1 is a diagram showing the relationship between the elongation of a cold-rolled steel plate and the temperature range in which the slab stays for 5 minutes or more at intervals of 50°C in the thermal history up to the start of rolling. Figure 2 shows the relationship between f and El and the residence time of the slab at 1150 to 950°C until the start of hot rolling.
A diagram showing the relationship between residence time at 50 to 950°C and aging index.
Figure 5 showing the relationship between residence time at °C and edge cracking of hot rolled sheet.
The figure shows the relationship between the slab thickness and the f value of a cold-rolled steel sheet. Patent applicant: Nippon Steel Corporation Temperature range (0C) //θa 'C-kai4υte' Ri no Kasate number; side) Fig. 5 θ 20 # u J
Fusamaubon 4yo (m 晟) Procedural amendment (spontaneous) June 10, 1985 Commissioner of the Patent Office Kuro 1) Akio Yu 1, Indication of the case 1986 Patent Application No. 90053 2, Processing of the name of the invention Manufacturing method for cold-rolled steel sheets with excellent properties 3 and its relationship with the amended case Patent applicant 2-6-3 Otemachi, Chiyoda-ku, Tokyo (665) Representative of Nippon Steel Corporation 1) Yutaka Takeshi 4. Agent Address: 2-4-1-6 Marunouchi, Chiyoda-ku, Tokyo 100 Japan, Claims column of the specification subject to amendment and Detailed Description of the Invention column 7, Contents of amendment, <--- /,;
-,,,. (1) Amend the claims as shown in the attached sheet. (2) Bottom line of page 3 of the specification r Mn: 0.05-0.
50%" is corrected to "Mn: 0.07 to 0.50%." (3) Table 1 on page 12 shall be amended as shown in the attached sheet. Claims (C: 0.070% or less at 11% by weight, Mn: 0.07
~0.50%, S: 0.015% or less, An:
0.005~0.100%, the balance being iron and unavoidable impurities, and when making a slab of 20~80mm thick, and hot rolling this slab immediately after solidification, a rolling steel of 1150~9
A method for producing a cold-rolled steel sheet with excellent workability, which comprises staying in a temperature range of 50° C. for 3 to 60 minutes, followed by hot rolling, followed by cold rolling and annealing. (2) C: 0.070% or less, Mn: 0 in weight%
．． 07-0.50%, S: 0.015% or less, A
l 70.005~0, 100% plus B 0.3
Molten steel containing ≦B/N≦1.5 with the remainder consisting of iron and inevitable impurities is made into a slab with a thickness of 20 to 80 nm,
When hot rolling this slab immediately after solidification, 1150~
A method for producing a cold-rolled steel sheet with excellent workability, which comprises staying in a temperature range of 950° C. for 3 to 60 minutes, followed by hot rolling, followed by cold rolling and annealing.
Claims (2)
〜０．５０％、Ｓ：０．０１５％以下、Ａｌ：０．００
５〜０．１００％、残部が鉄および不可避的不純物から
なる溶鋼を２０〜８０ｍｍ厚の鋳片とし、この凝固直後
の鋳片を熱間圧延するに際し、１１５０〜９５０℃の温
度域に３分〜６０分滞在せしめた後に熱間圧延し、引続
いて冷間圧延、焼鈍することを特徴とする加工性の優れ
た冷延鋼板の製造法。(1) C: 0.070% or less, Mn: 0.05 in weight%
~0.50%, S: 0.015% or less, Al: 0.00
Molten steel consisting of 5% to 0.100%, the balance being iron and unavoidable impurities is made into a slab with a thickness of 20 to 80mm, and when hot rolling the slab immediately after solidification, it is heated in a temperature range of 1150 to 950°C for 3 minutes. A method for producing a cold-rolled steel sheet with excellent workability, which comprises hot rolling after staying for ~60 minutes, followed by cold rolling and annealing.
〜０．５０％、Ｓ：０．０１５％以下、Ａｌ：０．００
５〜０．１００％に加えて、Ｂを０．３≦Ｂ／Ｎ≦１．
５の範囲で含有し、残部が鉄および不可避的不純物から
なる溶鋼を２０〜８０ｍｍ厚の鋳片とし、この凝固直後
の鋳片を熱間圧延するに際し、１１５０〜９５０℃の温
度域に３分〜６０分滞在せしめた後に熱間圧延し、引続
いて、冷間圧延、焼鈍することを特徴とする加工性の優
れた冷延鋼板の製造法。(2) C: 0.070% or less, Mn: 0.05 in weight%
~0.50%, S: 0.015% or less, Al: 0.00
In addition to 5 to 0.100%, B is 0.3≦B/N≦1.
The molten steel is made into a slab with a thickness of 20 to 80 mm, and when hot rolling the slab immediately after solidification, it is heated in a temperature range of 1150 to 950°C for 3 minutes. A method for producing a cold-rolled steel sheet with excellent workability, which comprises hot rolling after staying for ~60 minutes, followed by cold rolling and annealing.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9005386A JPH0692619B2 (en) | 1986-04-21 | 1986-04-21 | Manufacturing method of cold rolled steel sheet with excellent workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9005386A JPH0692619B2 (en) | 1986-04-21 | 1986-04-21 | Manufacturing method of cold rolled steel sheet with excellent workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62270726A true JPS62270726A (en) | 1987-11-25 |
| JPH0692619B2 JPH0692619B2 (en) | 1994-11-16 |
Family
ID=13987848
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9005386A Expired - Lifetime JPH0692619B2 (en) | 1986-04-21 | 1986-04-21 | Manufacturing method of cold rolled steel sheet with excellent workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0692619B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63241121A (en) * | 1987-03-28 | 1988-10-06 | Nippon Steel Corp | Manufacture of cold rolled steel sheet having superior workability |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013251672A (en) * | 2012-05-31 | 2013-12-12 | Seiko Epson Corp | Vibration piece, electronic device, electronic apparatus and manufacturing method for vibration piece |
-
1986
- 1986-04-21 JP JP9005386A patent/JPH0692619B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63241121A (en) * | 1987-03-28 | 1988-10-06 | Nippon Steel Corp | Manufacture of cold rolled steel sheet having superior workability |
| JPH0422972B2 (en) * | 1987-03-28 | 1992-04-21 | Nippon Steel Corp |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0692619B2 (en) | 1994-11-16 |
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| EXPY | Cancellation because of completion of term |