JPS63121623A - Production of cold rolled steel sheet for deep drawing having excellent ridging resistance and chemical convertibility - Google Patents
Production of cold rolled steel sheet for deep drawing having excellent ridging resistance and chemical convertibilityInfo
- Publication number
- JPS63121623A JPS63121623A JP26665186A JP26665186A JPS63121623A JP S63121623 A JPS63121623 A JP S63121623A JP 26665186 A JP26665186 A JP 26665186A JP 26665186 A JP26665186 A JP 26665186A JP S63121623 A JPS63121623 A JP S63121623A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- steel
- cold
- temperature
- steel sheet
- 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
- 239000000126 substance Substances 0.000 title claims abstract description 22
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 16
- 238000004519 manufacturing process Methods 0.000 title claims description 14
- 238000005098 hot rolling Methods 0.000 claims abstract description 25
- 238000000137 annealing Methods 0.000 claims abstract description 20
- 238000005097 cold rolling Methods 0.000 claims abstract description 17
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 16
- 239000010687 lubricating oil Substances 0.000 claims abstract description 8
- 238000001953 recrystallisation Methods 0.000 claims abstract description 8
- 229910001209 Low-carbon steel Inorganic materials 0.000 claims abstract description 6
- 238000006243 chemical reaction Methods 0.000 claims description 17
- 238000011282 treatment Methods 0.000 claims description 17
- 230000009467 reduction Effects 0.000 claims description 12
- 229910000831 Steel Inorganic materials 0.000 abstract description 37
- 239000010959 steel Substances 0.000 abstract description 37
- 238000000034 method Methods 0.000 abstract description 25
- 230000007547 defect Effects 0.000 abstract description 3
- 238000005096 rolling process Methods 0.000 description 36
- 238000010438 heat treatment Methods 0.000 description 14
- 230000000694 effects Effects 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 238000005461 lubrication Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 239000002244 precipitate Substances 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 230000006872 improvement Effects 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 230000001105 regulatory effect Effects 0.000 description 4
- 238000011160 research Methods 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 238000009749 continuous casting Methods 0.000 description 3
- 238000005554 pickling Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910000147 aluminium phosphate Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000002791 soaking Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000002023 wood Substances 0.000 description 2
- 229910019142 PO4 Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000010306 acid treatment Methods 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000004534 enameling Methods 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- -1 iron ions Chemical class 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000002480 mineral oil Substances 0.000 description 1
- 235000010446 mineral oil Nutrition 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 239000010452 phosphate Substances 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 102220082323 rs35269563 Human genes 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 238000010301 surface-oxidation reaction Methods 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 230000008961 swelling Effects 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 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】
（産業上の利用分野）
本発明は、耐リジング性と化成処理性とに優れる深絞り
用冷延鋼板の製造方法に関し、鋼の成分組成と圧延条件
を規制することにより、低温加熱−低温熱間圧延を可能
として上記の各性質を発現させる有効な研究成果につい
ての提案である。[Detailed Description of the Invention] (Industrial Application Field) The present invention relates to a method for producing cold-rolled steel sheets for deep drawing that have excellent ridging resistance and chemical conversion treatment properties, and involves regulating the composition and rolling conditions of the steel. This is a proposal for effective research results that enable low-temperature heating and low-temperature hot rolling to express each of the above properties.
自動車のパネルなどとして主に使用される冷延鋼板は、
その特性として浸れた深絞り性が要求される。深絞り性
向上のためには、鋼板の機械的特性として高い延性と高
いランクフォード値（ｒ値）が必要である。また、自動
車用外板などのように深絞り成形製品は外表面となるこ
とが多いので、表面性状に（盛れていることも重要な性
質であり、さらに焼付塗装の前処理である化成処理性も
重要である。Cold-rolled steel sheets are mainly used for automobile panels, etc.
Its properties require deep drawability. In order to improve deep drawability, the mechanical properties of the steel sheet need to be high ductility and high Lankford value (r value). In addition, since deep-drawn products such as automobile outer panels are often used as the outer surface, the surface quality (swelling) is also an important property, and chemical conversion treatment, which is a pretreatment for baking painting, is also important. It is also important.
ところで近年鉄鋼材料の製造工程は著しく変化し、深絞
り用薄鋼板の場合も例外ではない。つまり、在来は鋼を
造塊−分塊圧延にて２５０ｍｍ板厚程度の鋼片とした後
、加熱炉にて加熱均熱処理し、粗圧延工程により約３Ｑ
ｍｍ板厚のシートバーとし、さらに熱伝性」二温度が后
、変態点以上となるように仕上熱延工程にて所定板厚の
熱延鋼帯としていたが、近年まず連続鋳造プロセスの導
入により分塊圧延工程が省略可能となり、また溶鋼から
直ちに板厚５０ｍｍ以下のシートバーないし鋼帯を得る
手法により、熱間圧延の加熱処理及び粗圧延工程も省略
し得るという新しいプロセスも現実化しつつある。しか
しながらこれら新製造工程はいずれも溶鋼が凝固する際
にできる組織（鋳造組織）を破壊するという点では不利
である。とくに凝固時に形成された（１００ｊ＜ｕｖｗ
＞を主方位とする強い鋳造集合組織を破壊することはき
わめて困難である。Incidentally, the manufacturing process of steel materials has changed significantly in recent years, and the case of thin steel sheets for deep drawing is no exception. In other words, conventionally, steel is made into slabs with a thickness of about 250 mm by ingot making and blooming rolling, then heated and soaked in a heating furnace, and then rough rolled for about 3Q.
mm thick sheet bar, and in order to further improve thermal conductivity, the hot-rolled steel strip was made into a predetermined thickness in the finishing hot-rolling process so that the temperature reached the transformation point or higher, but in recent years, the continuous casting process has been introduced. This makes it possible to omit the blooming and rolling process, and a new process is also becoming a reality in which the hot rolling heat treatment and rough rolling processes can also be omitted by using a method to immediately obtain sheet bars or steel strips with a thickness of 50 mm or less from molten steel. be. However, all of these new manufacturing processes are disadvantageous in that they destroy the structure (casting structure) formed when molten steel solidifies. Especially formed during solidification (100j<uvw
It is extremely difficult to destroy the strong casting texture whose main orientation is >.
その結果、最終薄鋼板にはりジングが起こりやすくなり
、プレス加工など変形を受けると圧延方向に伸びた明瞭
な凹凸が生じて製品価値を損なうことになる。As a result, the final thin steel sheet tends to be prone to creasing, and when subjected to deformation such as press working, clear irregularities extending in the rolling direction occur, which impairs product value.
翻って在来の深絞り用冷延鋼板の製造では熱間圧延の仕
上温度を高温にする必要がある。そのため、高温スラブ
加熱、高温熱延を余儀なくされたわけであるが、高温ス
ラブ加熱は加熱エネルギー費用の上昇、スラブ表面酸化
による歩留りの低下、そして内部酸化生成物の増加によ
る品質上の問題、さらには冷間圧延でのトラブルの発生
などをもたらす不都合があった。また高温の熱間圧延は
圧延ロールの損傷等をひき起こしやすく、表面品質を劣
化させる原因でもあった。On the other hand, in the production of conventional cold-rolled steel sheets for deep drawing, it is necessary to raise the finishing temperature of hot rolling to a high temperature. Therefore, high-temperature slab heating and high-temperature hot rolling were unavoidable, but high-temperature slab heating increases heating energy costs, reduces yield due to slab surface oxidation, and causes quality problems due to an increase in internal oxidation products. This had the disadvantage of causing troubles during cold rolling. Further, hot rolling at high temperatures tends to cause damage to the rolling rolls, which is also a cause of deterioration of surface quality.
これに対し、低温スラブ加熱および低温熱間圧延により
、良好な深絞り性を有する冷延鋼板が製造できれば、上
記問題点は一掃でき、製造」二のメリットは大きい。On the other hand, if a cold-rolled steel sheet with good deep drawability can be produced by low-temperature slab heating and low-temperature hot rolling, the above-mentioned problems can be eliminated, and the second advantage in production is significant.
（従来の技術）
実際に、低温の熱間圧延による深絞り鋼板の製造方法は
既にいくつかが開示されており、例えば特開昭５７−１
３１２３号、特開昭５９−６７３２２号各公報などがそ
の例である。これらはいずれも低温加熱−低温熱間圧延
をすることを特徴とし、省エネルギー、材質向上面にお
いて有利である。しかしながら、これら公知技術は、前
述の耐リジング性および化成処理性を向上させる手法に
対しては何の示唆も与えるところがなく、しかも一般的
には、薄鋼板の耐リジング性に関しては、低温加熱−低
温熱間圧延の方が高温加熱−高温熱間圧延の場合よりも
不利である。(Prior Art) In fact, several methods for producing deep-drawn steel sheets by low-temperature hot rolling have already been disclosed, such as JP-A-57-1
Examples include No. 3123 and Japanese Unexamined Patent Publication No. 59-67322. All of these are characterized by low-temperature heating and low-temperature hot rolling, and are advantageous in terms of energy saving and improved material quality. However, these known techniques do not provide any suggestions for improving the above-mentioned ridging resistance and chemical conversion treatment properties, and in general, regarding the ridging resistance of thin steel sheets, low-temperature heating - Low temperature hot rolling is more disadvantageous than high temperature heating-high temperature hot rolling.
かかる熱間右よび冷間圧延では、ロール表面に潤滑油を
散布して圧延する潤滑圧延が行われ、この潤滑圧延によ
り圧延荷重が大幅に減少することによる省エネルギー化
、銅帯表面性状の向上、ロール摩耗の減少などに有利で
あって、この目的にそって各種の潤滑油供給方法ならび
に潤滑油が考えられている。実際にも熱間圧延につき特
公昭５２−４６２号、特開昭５１−６２１６７号各公報
などが公知技術としてあげられる。In such hot rolling and cold rolling, lubrication rolling is performed in which lubricating oil is spread on the roll surface, and this lubrication rolling significantly reduces the rolling load, resulting in energy savings, improvement in the surface properties of the copper strip, This is advantageous in reducing roll wear, and various lubricant supply methods and lubricants have been considered for this purpose. In fact, regarding hot rolling, Japanese Patent Publication No. 52-462 and Japanese Unexamined Patent Application Publication No. 51-62167 are cited as known techniques.
しかしながら、これらはいずれも熱間域（通常仕上温度
Ａｒ３点以上）での使用についてのものであり、本発明
における低温熱延域（仕上温度Ａｒ３点以下）での使用
とは異なるものであって、さらには耐リジング性と化成
処理性を向上させる手法に何ら示唆を与えるものでもな
かった。However, all of these are for use in the hot region (normal finishing temperature Ar 3 points or higher), which is different from the use in the low-temperature hot rolling region (finishing temperature Ar 3 points or lower) in the present invention. Moreover, it did not provide any suggestions on methods for improving ridging resistance and chemical conversion treatment properties.
一方、特開昭６１−１１９６２１号公報では、Ｃ：０．
００２ｗｊ％（以下は単に「％」で略記する）Ｎ：０．
００２１％、Ｓ：０．００８％、Ｔｉ：０．１０％にな
る鋼をＡｒ３変態点〜５５０℃の温度域にて潤滑油を用
いて合計圧下率が８３％の圧延を行い、ひき続き７５％
の冷間圧延を行い、その後連続焼鈍を行うことにより、
下＝ １．９３の特性を有する冷延鋼板の製造方法を提
案している。しかしながら、上記公知技術では、へｒ３
変態点〜５５０℃の低温域において８３％もの高圧下率
で圧延を施すため、そのために要するエネルギーは莫大
なものとなり、低温加熱による省エネルギーがなされて
も、そのメリットは少ない。さらに、得られるＴ値も２
．０未満であり、深絞り性を十分に満たしてはいない。On the other hand, in Japanese Patent Application Laid-open No. 119621/1983, C: 0.
002wj% (hereinafter simply abbreviated as "%") N: 0.
0021%, S: 0.008%, Ti: 0.10% was rolled using lubricating oil at a temperature range of Ar3 transformation point to 550°C with a total reduction rate of 83%. %
By cold rolling and then continuous annealing,
A method for manufacturing a cold rolled steel sheet having a property of 1.93 is proposed. However, in the above-mentioned known technology, her3
Since rolling is performed at a high reduction rate of 83% in a low temperature range from the transformation point to 550°C, the energy required for this is enormous, and even if energy can be saved by low-temperature heating, the benefits are small. Furthermore, the obtained T value is also 2
．． It is less than 0, and the deep drawability is not fully satisfied.
（発明が解決しようとする問題点）
例示した従来技術；例えば特開昭６１−１１９６２１号
公報などで提案しているＴｉ、 Ｎｂｔ加鋼を使用する
技術の場合、上述した問題点とともにＥβも劣るという
問題点を抱えていた。(Problems to be Solved by the Invention) Examples of the conventional technology; For example, in the case of the technology using Ti and Nbt processed steel proposed in JP-A-61-119621, etc., the Eβ is inferior as well as the above-mentioned problems. I had this problem.
これに対し本発明者らは、先に、未公開の特願昭６０−
１０９２３３号明細書において、Ｃ：０．００４％、Ｎ
： ０．００２９％、Ｓ：０．００２ ％、Ｔｉ：０
．０３２ ％なる鋼を、加熱温度１０００℃、仕上温度
７１０℃で潤滑圧延後、７５％の冷延および焼鈍を施す
ことにより、下−２，２、Ｅ Ｚ＝５１（％）でかつ耐
リジング性と化成処理性に優れる冷延鋼板の製造方法を
提案した。In contrast, the present inventors previously proposed an unpublished patent application filed in 1983-
In specification No. 109233, C: 0.004%, N
: 0.0029%, S: 0.002%, Ti: 0
．． 032% steel is lubricated rolled at a heating temperature of 1000°C and a finishing temperature of 710°C, and then cold rolled and annealed to 75%, resulting in lower -2.2, E Z = 51 (%) and ridging resistance. We proposed a method for manufacturing cold-rolled steel sheets with excellent chemical conversion treatment properties.
しかしながら、この先行提案にかかる技術も得られる「
１直は高々２．２であるため、超深絞り性が要求される
部位に使用さる場合には、より以上に浸れた深絞り性が
必要である。However, the technology related to this advance proposal can also be obtained.
Since one stroke is at most 2.2, when used in areas that require ultra-deep drawability, it is necessary to have even greater deep drawability.
そこで本発明では、鋼の成分組成を規制するとともに、
低温加熱−低温熱間圧延を施すと言う方法に着目して耐
リジング性と化成処理性とに優れる深絞り用冷延鋼板の
製造方法の開発を目指したのである。Therefore, in the present invention, while regulating the chemical composition of steel,
Focusing on the method of applying low-temperature heating and low-temperature hot rolling, the aim was to develop a method for manufacturing cold-rolled steel sheets for deep drawing that has excellent ridging resistance and chemical conversion treatment properties.
（問題点を解決するための手段）
」１掲の問題点に対し本発明は、
Ｔ１添加による析出物は主としてＴｉ（Ｃ，Ｎ、 Ｓ）
なる複合物であるという知見をもとにこの複合物を固
定するのに要する必要最小限のＴｌ量を、Ｃ，Ｎ。(Means for Solving the Problems) In order to solve the problems listed in item 1, the present invention provides that the precipitates due to the addition of T1 are mainly Ti (C, N, S).
Based on the knowledge that the composite is composed of C and N, the minimum amount of Tl required to fix this composite was determined by C and N.
Ｓとの関連において制（卸するという前世、そして好適
量のＮｂおよびＢの添加を行うという着１世をもとに合
金設計をした累財を用いると、母板結晶粒の微細化やＥ
β、ｒ値の一層の向上が実現できるという点の知見にも
とづくものである。In relation to S, if we use the alloy design based on the previous life of controlling (wholesale) and the first generation of adding appropriate amounts of Nb and B, it is possible to refine the mother plate grains and
This is based on the knowledge that further improvements in β and r values can be realized.
ずなわら、本発明は、
Ｃ５０，００５％、Ｎ≦０．００５ ｗｔ％Ｓ≦０．０
０７％を含み、
Ｔｉ： ０．０１〜０．０５％で、かつＣ，Ｎ及びＳの
合計型がＴｉ量との関係において２≦Ｔｉ ／ （Ｃ＋
Ｎ ＋Ｓ）≦５Ｎｂ
：０．００１〜０．０２％、Ｂ：０．０ＯＯ１〜０．０
０２％を含有する低炭素鋼を、所定阪厚に熱間圧延する
際、仕上温度を６００〜８００ ℃とし、かつ少なくと
も１バスでは潤滑油を用いて仕上げ、ひき続き圧下率５
０〜９５％で冷間圧延し、次に再結晶焼鈍することを特
徴とする耐リジング性と化成処理性に１盛れる深絞り用
冷延鋼板の製造方法を要旨
構成とする。However, the present invention has the following characteristics: C50,005%, N≦0.005 wt%S≦0.0
07%, Ti: 0.01 to 0.05%, and the total type of C, N, and S satisfies 2≦Ti/(C+
N+S)≦5Nb: 0.001-0.02%, B: 0.0OO1-0.0
When hot rolling low carbon steel containing 0.02% to a specified thickness, the finishing temperature is 600 to 800°C, and at least one bath is finished using lubricating oil, and the rolling reduction is 5.
The gist of the present invention is a method for producing a cold-rolled steel sheet for deep drawing, which is characterized by cold rolling at 0 to 95% and then recrystallization annealing, which has both ridging resistance and chemical conversion treatment properties.
（作 用）
先に提案した前記特願昭６０−１０９２３３号明細書に
て、開示したように低炭素鋼を所定板厚に熱間圧延する
際、仕上温度を６００〜８００℃とし、かつ少なくとも
１パスでは潤滑油を用いて仕上げ、ひき続き圧下率５０
〜９５％で冷間圧延し、次に再結晶焼鈍すると、耐リジ
ング性と化成処理性に優れる深絞り用冷延鋼板が製造で
きることを見出したが、その後本発明者らがさらに研究
を重ねた結果、素財の低炭素鋼の成分組成を規制するこ
とにより、より一層の深絞り性を有する冷延鋼板が製造
可能となることを見出した。(Function) As disclosed in the previously proposed Japanese Patent Application No. 109233/1983, when hot rolling low carbon steel to a predetermined thickness, the finishing temperature is set at 600 to 800°C, and at least Finished with lubricating oil in the first pass, and then continued with a reduction rate of 50.
It was discovered that by cold rolling at ~95% and then recrystallization annealing, it was possible to produce cold rolled steel sheets for deep drawing with excellent ridging resistance and chemical conversion treatment properties, but the inventors subsequently conducted further research. As a result, they discovered that by regulating the composition of the raw low-carbon steel, it is possible to produce cold-rolled steel sheets with even greater deep drawability.
本発明を開発するに至る基礎とな、った研究結果は以下
のとおりである。The research results that formed the basis for developing the present invention are as follows.
Ｃ：０．００２〜０．００４％、Ｎ：０．００２〜０．
００４％、Ｓ：０．００２〜０．００５％、Ｔｉ： Ｑ
〜０．１０％、Ｎｂ ： ０．００７％およびＢ ：
０．０００８％なる成分組成の鋼片を、加熱温度１１０
０℃、仕上温度７００℃、３パス、圧下率９０％で潤滑
圧延し、酸洗後圧工率７５％で冷間圧延した。C: 0.002-0.004%, N: 0.002-0.
004%, S: 0.002-0.005%, Ti: Q
~0.10%, Nb: 0.007% and B:
A steel piece with a composition of 0.0008% was heated to a temperature of 110
Lubricated rolling was carried out at 0° C. and finishing temperature of 700° C. for 3 passes at a rolling reduction of 90%, and after pickling, cold rolling was carried out at a rolling reduction of 75%.
第１図にこの時のＴ＋／（Ｃ＋Ｎ ＋ｓ）の値ど焼鈍後
（均熱温度８３０℃）のＥ！およびｒ値の関係を示す。Figure 1 shows the values of T+/(C+N +s) at this time and E! after annealing (soaking temperature 830°C). and the relationship between the r value.
この図かられかるように、焼鈍後の鋼板のＥβおよびＴ
値は、Ｔｉ／（Ｃ＋ Ｎ＋ Ｓ ）の値に強く依存して
おり、Ｅ！≧５２％かつ下≧２．２なる特性を満たずた
めには、この関係は２≦Ｔｉ／（Ｃ＋ Ｎ ＋ Ｓ ）
≦５であることが必要であることを見出した。なお、耐
リジング性および化成処理性は、先行して提案した特願
昭６０−１０９２３３号の明細書で示した如く、本発明
においても優れていた。As can be seen from this figure, Eβ and T of the steel plate after annealing
The value strongly depends on the value of Ti/(C+N+S) and E! In order to satisfy the characteristics of ≧52% and lower≧2.2, this relationship is 2≦Ti/(C+N+S)
It has been found that it is necessary that ≦5. In addition, the ridging resistance and chemical conversion treatment properties were also excellent in the present invention, as shown in the specification of Japanese Patent Application No. 109233/1988, which was previously proposed.
本発明者らはこの基礎的データに基づきさらに研究を重
ねた結果、以下のように；製造条件をも規制すると深絞
り性と耐リジング性と化成処理性に１多れる薄鋼板が製
造できることを究明したのである。As a result of further research based on this basic data, the inventors of the present invention found that if the manufacturing conditions were also regulated, it was possible to manufacture a thin steel sheet with improved deep drawability, ridging resistance, and chemical conversion treatment properties. I investigated it.
以下に鋼組成、圧延累材、熱間−冷間圧延および焼鈍の
各条件について具体的に説明する。The steel composition, rolling stock, hot-cold rolling, and annealing conditions will be specifically explained below.
（１） 鋼組成について、
（ａ） Ｃ５０，００５％
Ｃは、少ない程深絞り性が向上するので好ましいが、０
．００５９６以下の含有量だと、深絞り性に悪影響を及
ぼさないので、Ｃ≦０．００５％と限定した。(1) Regarding the steel composition: (a) C50,005% C is preferable because the less it is, the better the deep drawability is, but 0
．． Since a content of 00596 or less does not have an adverse effect on deep drawability, it is limited to C≦0.005%.
（ｂ） Ｎ ：０．００５９６
Ｎは、少ない程深絞り性が向上するので好ましいが、０
．００５％以下の含有量だと深絞り性に悪１１’＆ Ｋ
を及ぼさないので、Ｎ≦０．００５％と限定した。(b) N: 0.00596 N is preferable because the less it is, the better the deep drawability is.
．． If the content is less than 0.005%, the deep drawability will be poor11'&K
Therefore, it was limited to N≦0.005%.
（Ｃ） Ｓ、： ０．００７％
Ｓは、少ない程深絞り性が向上するので好ましいが、０
．００７％以下の含有量だと深絞り性に悪影響を及ぼさ
ないので、Ｓ≦０．００７％と限定した。(C) S: 0.007% S is preferable because the smaller the amount, the better the deep drawability is.
．． Since a content of 0.007% or less will not have an adverse effect on deep drawability, it is limited to S≦0.007%.
（ｄ） ０．０１≦Ｔｉ≦０，０５％Ｔ１は、炭化物
、窒化物、硫化物を形成し、鋼中の固溶Ｃ，Ｎを減少さ
せることにより深絞り性を向上させるために添加含有さ
せる。(d) 0.01≦Ti≦0.05%T1 is added to improve deep drawability by forming carbides, nitrides, and sulfides and reducing solid solution C and N in the steel. let
しかしながら、その含有量が０．０１％未満では所望の
効果が得られず、一方０．０５％を超えて含有させると
、延性が劣化するので、０．旧≦Ｔ１≦０．０５％に限
定した。However, if the content is less than 0.01%, the desired effect cannot be obtained, while if the content exceeds 0.05%, the ductility deteriorates. It was limited to old≦T1≦0.05%.
さらに、この１１塁については、Ｃ，ＮおよびＳの合計
含有量に対する関係が、２≦Ｔｉ／（Ｃ＋Ｎ＋Ｓ）≦５
でなければ、深絞り性および延性の両方の特性を満たず
ことはできない。２ （Ｃ４−Ｎ＋Ｓ）＞’ｒｉでは鋼
中に固溶Ｃ１Ｎが残（ｒするために深絞り性が劣り、一
方′ｒＩ＞５（Ｃ十Ｎ←Ｓ）では鋼中に固溶Ｔｉが多量
に残存するため、延性が劣化するためであると考えられ
る。さらに、Ｔｉ （Ｃ，Ｎ、 Ｓ）の析出物の形態
およびその数量も深絞り性および延性に影響を与えるも
のと考えられる。Furthermore, regarding this 11th base, the relationship with respect to the total content of C, N, and S is 2≦Ti/(C+N+S)≦5
Otherwise, it is impossible to satisfy both the characteristics of deep drawability and ductility. 2 When (C4-N+S)>'ri, solid solute C1N remains in the steel, resulting in poor deep drawability; on the other hand, when 'rI>5 (C0N←S), a large amount of solid solute Ti remains in the steel. This is thought to be because the ductility deteriorates as the Ti (C, N, S) precipitates remain in the Ti (C, N, S) precipitates.Furthermore, the form and quantity of Ti (C, N, S) precipitates are also thought to affect deep drawability and ductility.
（ｅ） ０．０（Ｈ≦Ｎｂ≦０．０２％Ｎｂは、熱延
板を細粒化し、冷延−焼鈍後の深絞り性向上および異方
性改善の効果があるので添加する。その含有量が０．０
０１ ％未満では所望の効果が得られず、一方、０．０
２％を越えて添加すると、延性が著しく劣化するので、
０．００１ ≦Ｎ’ｂ≦０，０２％に限定した。(e) 0.0 (H≦Nb≦0.02%Nb is added because it has the effect of making the hot rolled sheet finer and improving the deep drawability and anisotropy after cold rolling and annealing. Content is 0.0
If it is less than 0.01%, the desired effect cannot be obtained;
If it is added in excess of 2%, the ductility will be significantly deteriorated.
It was limited to 0.001≦N'b≦0.02%.
（ｆ） ０．０００１ ≦Ｂ ≦０．００２ ％Ｂ
は、延性を向上させ、かつ二次加工脆性を改善する効果
があるので添加するが、その含有量が０．００旧％未満
では所望の効果が得られず、一方０．００２％を越えて
添加すると、深絞り性が劣化ずので、０．０００１≦Ｂ
≦０．００２％に限定した。(f) 0.0001 ≦B ≦0.002 %B
is added because it has the effect of improving ductility and improving secondary work brittleness, but if its content is less than 0.00%, the desired effect cannot be obtained, while if it exceeds 0.002% When added, deep drawability does not deteriorate, so 0.0001≦B
It was limited to ≦0.002%.
（２） 圧延窓１才について、
圧延素材は、造塊−分塊圧延又は連続鋳造法の如き従来
方式により得られる鋼片は当然適用でき、この場合鋼片
の加熱温度は８００〜１２５０℃が適当であり、とくに
９５０〜１１５０℃が好適である。連続鋳造から鋼片を
再加熱することなく圧延を開始する、連続鋳造−直接圧
延法くいわゆるｃｃ−ｏｒｔ法）も適用可能なのは勿論
である。(2) For rolling windows of 1 year old, steel slabs obtained by conventional methods such as ingot-blowing rolling or continuous casting can be used as the rolled material, and in this case, the heating temperature of the steel slabs should be 800 to 1250°C. The temperature is suitable, particularly 950 to 1150°C. Of course, a continuous casting-direct rolling method (so-called CC-ORT method), in which rolling is started without reheating the steel billet after continuous casting, is also applicable.
一方、溶鋼から直接５０ｍｍ以下の圧延素材を鋳造する
方法（シートバーキャスター法およびストリップキャス
ター法）も省エネルギー、省工程の観点から経済的メリ
ットが大きく、もとよりこの発明の圧延素材の製造には
と（に有利である。On the other hand, methods of directly casting rolled material of 50 mm or less from molten steel (sheet bar caster method and strip caster method) also have great economic merits from the viewpoint of energy saving and process saving, and are of course suitable for manufacturing the rolled material of this invention. advantageous to
（３） 熱間圧延 この工程は、本発明において極めて重要である。(3) Hot rolling This step is extremely important in the present invention.
仕上げ圧延を６００℃〜８００℃の温度範囲とし、かつ
少なくとも１パスでは潤滑を用いて仕」こげすることが
必須である。It is essential that the finish rolling be carried out at a temperature range of 600° C. to 800° C., and that lubrication be used in at least one pass.
仕上げ圧延温度が８００℃以上の高温域では、高温熱延
における諸問題が生じてこの発明における低温熱間圧延
に基づくメリットは少ない。When the finish rolling temperature is in a high temperature range of 800° C. or higher, various problems occur in high temperature hot rolling, and there are few merits based on low temperature hot rolling in this invention.
またこの仕上げ圧延温度は、６００ を以下で、圧延荷
重の急−１−昇を来たし、省エネルギーの観点からもメ
リットは少ない。Moreover, when the finish rolling temperature is below 600° C., the rolling load suddenly increases by 1-1, and there is little merit from the viewpoint of energy saving.
熱間圧延後の巻取温度は特に限定されないが、酸洗効率
を向上させるために６００℃以下が好ましい。The coiling temperature after hot rolling is not particularly limited, but is preferably 600° C. or lower in order to improve pickling efficiency.
圧延パス数、圧下率の配分は、少なくともｌパスでは潤
滑下に仕上げる条件を満たす限り任意でよく、もちろん
圧延機の配列構造、ロール径、張力なども木質的な影響
力を持たない。The number of rolling passes and the distribution of the rolling reduction ratio may be arbitrary as long as the conditions for finishing with lubrication are satisfied in at least one pass, and of course the arrangement structure of the rolling mill, roll diameter, tension, etc. do not have any influence on wood quality.
潤滑油の種類および散布方法についてもこの発明におい
ては限定されるものではない。鉱油をベースとする懸濁
ン市などを通常の方法にて適用することが好適である。The type of lubricating oil and the method of dispersing it are also not limited in this invention. It is preferred to apply mineral oil based suspensions or the like in the usual manner.
なお、潤滑圧延による耐リジング性さらには化成処理性
の向上については、以下の如く考えられる。すなわち、
Ａｒ３変態点以下で無潤滑圧延を行うと、冷延−焼？屯
後の鋼板表面にリジングが発生ずる。しかしながら、潤
滑圧延を行った場合には、加工歪の加わり方がｊ！■潤
滑圧延時と異なるために、鋳造集合組織が容易に破壊さ
れるものと考えられる。さらに、潤滑圧延を行った場合
には、冷延−焼鈍後の鋼板表面の集合組織がＮ、 ０．
／＜ＩＬＬ〉であるのに対し、ｆ（（（潤滑圧延時のそ
れがＮ、 Ｄ、／＜１１０＞であることが、化成処理性
向上に関係しているものと考えられる。The improvement in ridging resistance and chemical conversion treatment properties due to lubricated rolling is thought to be as follows. That is,
If rolling without lubrication is performed below the Ar3 transformation point, will cold rolling-sintering occur? Rigging occurs on the surface of the steel plate after finishing. However, when lubricated rolling is performed, the amount of processing strain is j! ■It is thought that the casting texture is easily destroyed because it is different from that during lubricated rolling. Furthermore, when lubricated rolling is performed, the texture of the steel sheet surface after cold rolling and annealing is N, 0.
/<ILL>, whereas f((((((()) during lubricated rolling is N, D, /<110>, which is considered to be related to improvement in chemical conversion treatment properties.
（４）冷間圧延
この工程も、この発明において必須であり、高いｒ値お
よび面内異方性を小さくするために、冷間圧下率は５０
〜９５％とすることが不可欠である。(4) Cold rolling This step is also essential in this invention, and in order to reduce the high r value and in-plane anisotropy, the cold rolling reduction rate is 50
~95% is essential.
冷延圧下率が５０％未満または９５％以上であると、優
れた深絞り性を得ることができない。If the cold rolling reduction is less than 50% or more than 95%, excellent deep drawability cannot be obtained.
（５） 焼 ２屯
冷間圧延工程を経た冷延鋼帯は、再結晶焼鈍が必要であ
る。焼鈍方法は箱型焼鈍法、連続型焼鈍法のいずれでも
よいが、均質性、生産性の観点から後者が有利である。(5) Annealing The cold-rolled steel strip that has undergone the 2-ton cold rolling process requires recrystallization annealing. The annealing method may be either a box annealing method or a continuous annealing method, but the latter is advantageous from the viewpoint of homogeneity and productivity.
加熱温度は再結晶温度（約６５０℃）から９５０℃の範
囲で適合する。なお、連続焼鈍の場合の熱サイクルにつ
いて均熱後の冷却速度、および過時効処理の有無とその
ヒートサイクルの如き条件は、この発明において木質的
な９背をおよぼさない。The heating temperature ranges from the recrystallization temperature (approximately 650°C) to 950°C. Regarding the heat cycle in the case of continuous annealing, conditions such as the cooling rate after soaking, the presence or absence of overaging treatment, and the heat cycle do not affect the wood quality in this invention.
焼鈍後の銅帯には形状矯正、表面粗度等の調整のために
１０％以下の調質圧延を加えることができる。The copper strip after annealing may be subjected to temper rolling of 10% or less in order to correct the shape and adjust the surface roughness.
なお、この発明で（尋られる冷延鋼板は、加工用表面鋼
板の原板としても適用でき、表面処理としては、亜鉛め
っき（合金系含む）、錫めっき、そしてほうろうなどが
ある。In addition, the cold-rolled steel sheet referred to in this invention can also be used as an original sheet for surface steel sheets for processing, and surface treatments include galvanizing (including alloy-based), tin plating, and enameling.
〈実施例）
表Ｉに示す化学組成の鋼片を、転炉製鋼一連続鋳造法に
より製造した。<Example> Steel slabs having the chemical compositions shown in Table I were produced by a continuous converter steelmaking method.
この鋼片を、９５０℃〜１１５０℃に加熱、均熱後、粗
圧延により２０〜３Ｑｍｍ板厚のシートバーとし、連続
的に７列からなる仕上圧延機を用いて３．２ｍｍ板厚の
熱延板とした。この時、全列の圧延機を用いて潤滑圧延
を行った。This steel billet was heated to 950°C to 1150°C, soaked, and then roughly rolled into a sheet bar with a thickness of 20 to 3 Qmm. It was made into a rolled plate. At this time, lubricated rolling was performed using all rows of rolling mills.
酸洗後、０．８ｍｍ板厚（冷延圧下率７５％）または１
、７ｍｍ板厚（冷延圧下率４７％）の冷延板とし、ひき
続き８３０℃−４０秒の再結晶焼鈍を施した。After pickling, 0.8 mm plate thickness (cold rolling reduction ratio 75%) or 1
A cold rolled plate having a thickness of 7 mm (cold rolling reduction ratio of 47%) was prepared, and then recrystallization annealing was performed at 830° C. for 40 seconds.
熱間圧延条件別に連続焼鈍後の祠科特性を表２に示す。Table 2 shows the abrasive properties after continuous annealing under different hot rolling conditions.
引張特性はＪＩＳ５号試験片として求めた。The tensile properties were determined using a JIS No. 5 test piece.
リジング性は圧延方向から切り出したＪＩ３５号試験片
を用いて１５％引張子ひずみを付加し、表面の凹凸を目
視法にて１（良）〜５（劣）の評価をした。評価１．２
は実用上問題のないリジング性を示す。The ridging property was evaluated using a JI No. 35 test piece cut out from the rolling direction, subjected to 15% tensile strain, and visually evaluated for surface irregularities on a scale of 1 (good) to 5 (poor). Rating 1.2
shows ridding properties that pose no problem in practical use.
化成処理性は鋼板を脱脂、水洗、リン酸塩処理を施し、
以下に述べるピンホールテストを行った時のピンホール
面積率と結晶析出数で評価した。For chemical conversion treatment, the steel plate is degreased, washed with water, and treated with phosphate.
Evaluation was made based on the pinhole area ratio and the number of crystal precipitates when performing the pinhole test described below.
なお、リン酸処理は日本パー力うイジングｃ勺製ＢＴ３
１１２を用い、５５℃で全酸度１４．３、遊離酸度０．
５に調整し、スプレーで１２０秒間吹付けた。In addition, the phosphoric acid treatment was performed using Nippon Parr Ising C. BT3.
112 at 55°C, total acidity 14.3, free acidity 0.
5 and sprayed for 120 seconds.
ピンホールテストは、試験面に鉄イオン出反応して発色
する試薬（フェロオキシル溶液）を浸したろ紙を密着さ
せて、鋼板表面に残留するリン酸結晶未付着部分を検知
し、それを画像解析してピンホール面積率として数値化
した。結晶析出数はＳ Ｅ Ｍ観察により行った。なお
、これら化成処理性の評価基準は以下のように定めた。In the pinhole test, a filter paper immersed in a reagent (ferrooxyl solution) that develops color when iron ions are released is placed in close contact with the test surface to detect areas where phosphoric acid crystals remain on the surface of the steel plate and perform image analysis. It was quantified as the pinhole area ratio. The number of crystals precipitated was determined by SEM observation. The evaluation criteria for chemical conversion treatment properties were determined as follows.
まずピンホール面積率は、２％未満を０，２〜９％では
Δ、９％超過について、×、または結晶析出数（ＸＩＯ
’／ｍｍ２）は、５以上で０，５未満３までがΔ、そし
て３未満では×として評価した。First, the pinhole area ratio is 0 for less than 2%, Δ for 2 to 9%, × or the number of crystal precipitation (XIO
'/mm2) was evaluated as 0 if it was 5 or more, Δ if it was less than 3, and × if it was less than 3.
本発明に従って得られた鋼板は、高いｒ値、Ｅｌを示す
とともに、浸れた耐リジング性と化成処理性を示してい
る。The steel sheets obtained according to the invention exhibit high r-values, El, as well as soaked ridging resistance and chemical conversion treatability.
（発明の効果）
以上の説明ならびに実施例の結果かられかるように本発
明によれば、冷延板に充てる熱間圧延の加工度の如何に
拘らず、リジング欠陥を発生ずるうれいなく深絞り性、
化成処理性の向上を図ることができるので、エネルギー
コストの低減に有効である。(Effects of the Invention) As can be seen from the above explanations and the results of the examples, according to the present invention, regardless of the degree of hot rolling applied to cold rolled sheets, ridging defects can be smoothly and deeply removed. Drawability,
Since it is possible to improve chemical conversion treatment properties, it is effective in reducing energy costs.
第１図は、Ｔｉ／（Ｃ＋ Ｎ＋ Ｓ ）とＥＮ、ｒ値と
の関係を示すグラフである。
第１図
一／（Ｃ＋Ｎ十Ｓ）FIG. 1 is a graph showing the relationship between Ti/(C+N+S), EN, and r value. Figure 1 1/(C+N10S)
Claims (1)
≦０．００７ｗｔ％を含み、 Ｔｉ：０．０１〜０．０５ｗｔ％で、かつ Ｃ、Ｎ及びＳの合計量がＴｉ量との関係において ２≦Ｔｉ／（Ｃ＋Ｎ＋Ｓ）≦５ Ｎｂ：０．００１〜０．０２ｗｔ％、Ｂ：０．０００１
〜０．００２ｗｔ％を含有する低炭素鋼を、所定板厚に
熱間圧延する際、仕上温度を６００〜８００℃とし、か
つ少なくとも１パスでは潤滑油を用いて仕上げ、ひき続
き圧下率５０〜９５％で冷間圧延し、次に再結晶焼鈍す
ることを特徴とする耐リジング性と化成処理性に優れる
深絞り用冷延鋼板の製造方法。[Claims] 1. C≦0.005wt%, N≦0.005wt%, S
≦0.007wt%, Ti: 0.01 to 0.05wt%, and the total amount of C, N, and S is 2≦Ti/(C+N+S)≦5 in relation to the Ti amount Nb: 0.001 ~0.02wt%, B:0.0001
When hot rolling low carbon steel containing ~0.002wt% to a predetermined thickness, the finishing temperature is 600~800°C, and at least one pass is finished using lubricating oil, followed by a reduction rate of 50~800°C. A method for producing a cold-rolled steel sheet for deep drawing, which has excellent ridging resistance and chemical conversion treatment properties, characterized by cold rolling at 95% and then recrystallization annealing.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26665186A JPS63121623A (en) | 1986-11-11 | 1986-11-11 | Production of cold rolled steel sheet for deep drawing having excellent ridging resistance and chemical convertibility |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26665186A JPS63121623A (en) | 1986-11-11 | 1986-11-11 | Production of cold rolled steel sheet for deep drawing having excellent ridging resistance and chemical convertibility |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63121623A true JPS63121623A (en) | 1988-05-25 |
| JPH0238648B2 JPH0238648B2 (en) | 1990-08-31 |
Family
ID=17433792
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP26665186A Granted JPS63121623A (en) | 1986-11-11 | 1986-11-11 | Production of cold rolled steel sheet for deep drawing having excellent ridging resistance and chemical convertibility |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63121623A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0247222A (en) * | 1988-08-05 | 1990-02-16 | Kawasaki Steel Corp | Production of cold-rolled steel sheet for super deep drawing |
| JPH0394021A (en) * | 1989-09-05 | 1991-04-18 | Kobe Steel Ltd | Production of cold rolled steel sheet excellent in deep drawability and resistance to secondary working brittleness |
| JPH09241755A (en) * | 1996-03-04 | 1997-09-16 | Kawasaki Steel Corp | Production of steel sheet excellent in deep drawability |
| US5846343A (en) * | 1995-03-16 | 1998-12-08 | Kawasaki Steel Corporation | Cold rolled steel sheet exhibiting excellent press workability and method of manufacturing the same |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5842752A (en) * | 1981-09-07 | 1983-03-12 | Nippon Steel Corp | Cold rolled steel plate with superior press formability |
| JPS59193221A (en) * | 1983-04-15 | 1984-11-01 | Nippon Steel Corp | Rreparation of cold rolled steel plate used in ultra-deep drawing having extremely excellent secondary processability |
| JPS61119621A (en) * | 1984-11-16 | 1986-06-06 | Nippon Steel Corp | Manufacture of cold rolled steel sheet for deep drawing |
| JPS61246344A (en) * | 1985-04-22 | 1986-11-01 | Kawasaki Steel Corp | Cold rolled steel sheet for super drawing excelling in resistance to secondary operation brittleness |
-
1986
- 1986-11-11 JP JP26665186A patent/JPS63121623A/en active Granted
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5842752A (en) * | 1981-09-07 | 1983-03-12 | Nippon Steel Corp | Cold rolled steel plate with superior press formability |
| JPS59193221A (en) * | 1983-04-15 | 1984-11-01 | Nippon Steel Corp | Rreparation of cold rolled steel plate used in ultra-deep drawing having extremely excellent secondary processability |
| JPS61119621A (en) * | 1984-11-16 | 1986-06-06 | Nippon Steel Corp | Manufacture of cold rolled steel sheet for deep drawing |
| JPS61246344A (en) * | 1985-04-22 | 1986-11-01 | Kawasaki Steel Corp | Cold rolled steel sheet for super drawing excelling in resistance to secondary operation brittleness |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0247222A (en) * | 1988-08-05 | 1990-02-16 | Kawasaki Steel Corp | Production of cold-rolled steel sheet for super deep drawing |
| JPH0394021A (en) * | 1989-09-05 | 1991-04-18 | Kobe Steel Ltd | Production of cold rolled steel sheet excellent in deep drawability and resistance to secondary working brittleness |
| JPH0784619B2 (en) * | 1989-09-05 | 1995-09-13 | 株式会社神戸製鋼所 | Method for producing cold-rolled steel sheet excellent in deep drawability and resistance to secondary work brittleness |
| US5846343A (en) * | 1995-03-16 | 1998-12-08 | Kawasaki Steel Corporation | Cold rolled steel sheet exhibiting excellent press workability and method of manufacturing the same |
| JPH09241755A (en) * | 1996-03-04 | 1997-09-16 | Kawasaki Steel Corp | Production of steel sheet excellent in deep drawability |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0238648B2 (en) | 1990-08-31 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| LAPS | Cancellation because of no payment of annual fees |