JPH073429A - Production of cold rolled steel sheet for deep drawing, excellent in dent resistance and surface strain resistance - Google Patents
Production of cold rolled steel sheet for deep drawing, excellent in dent resistance and surface strain resistanceInfo
- Publication number
- JPH073429A JPH073429A JP14955793A JP14955793A JPH073429A JP H073429 A JPH073429 A JP H073429A JP 14955793 A JP14955793 A JP 14955793A JP 14955793 A JP14955793 A JP 14955793A JP H073429 A JPH073429 A JP H073429A
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- Japan
- Prior art keywords
- less
- resistance
- steel sheet
- nitriding
- surface strain
- 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.)
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は耐デント性ならびに耐面
ひずみ性に優れた深絞り用冷延鋼板の製造方法に関する
ものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a cold-rolled steel sheet for deep drawing which is excellent in dent resistance and surface strain resistance.
【０００２】[0002]
【従来の技術】ＴｉやＮｂを極低炭素鋼に添加し、固溶
Ｃ、Ｎを炭窒化物の形で固定したＩＦ鋼板（Ｉｎｔｅｒ
ｓｔｉｔｉａｌ ａｔｏｍ ｆｒｅｅ ｓｔｅｅｌ ｓ
ｈｅｅｔ）は優れた深絞り性を有する冷延鋼板として広
く使用されている。しかし、この鋼板の弱点は軟質のた
め、耐面ひずみ性には優れているが、耐デント性が劣
り、自動車用の外板等に適用すると成形後外力を加える
と形状が容易に崩れる欠点がある。一方、耐デント性を
向上させるには降伏点を高めることが有効であることが
知られているが、この場合形状凍結性が悪くなり面ひず
みが生じやすくなる。耐デント性ならびに耐面ひずみ性
を有する鋼板の製造方法として最近表層をハイテン化し
た複層鋼板による製造方法を開示した特開平４−１４３
２２７号公報が有る。しかし、複層鋼板による製造法は
大幅なコスト増となり実用的でない。2. Description of the Related Art IF steel sheet (Inter steel sheet) in which Ti and Nb are added to ultra-low carbon steel and solid solution C and N are fixed in the form of carbonitride
stial atom free steels
Heet) is widely used as a cold-rolled steel sheet having excellent deep drawability. However, the weak point of this steel sheet is that it is soft and therefore excellent in surface strain resistance, but inferior in dent resistance, and when applied to automobile outer plates, etc., the shape easily collapses when external force is applied after molding. is there. On the other hand, it is known that increasing the yield point is effective for improving the dent resistance, but in this case, the shape fixability deteriorates and the surface strain easily occurs. As a method for producing a steel sheet having dent resistance and surface strain resistance, a method for producing a multi-layer steel sheet whose surface layer has been made high tenth has been disclosed recently.
There is a 227 publication. However, the production method using multi-layered steel plate is not practical because the cost increases significantly.
【０００３】一方、表面近傍層だけをハイテン化する方
法として、浸炭処理あるいは窒化処理がよく知られてお
り特開平３−２４３７５７号公報に浸炭・窒化処理によ
り表面近傍で強度の高い冷延鋼板ならびにその製造方法
が開示されている。しかし、優れた強度と加工性のバラ
ンスを得ることを課題としたために、耐デント性、耐面
ひずみ性に関して全く検討されておらず、耐デント性と
耐面ひずみ性を同時に満足する窒化鋼板ならびにその製
造方法についてまったく開示されていないだけでなく、
示唆する結果も提示されていない。On the other hand, a carburizing treatment or a nitriding treatment is well known as a method for increasing the tensile strength of only the near surface layer. JP-A-3-243757 discloses a cold rolled steel sheet having high strength near the surface by carburizing and nitriding treatment. A manufacturing method thereof is disclosed. However, in order to obtain a balance between excellent strength and workability, dent resistance and surface strain resistance have not been studied at all, and a nitrided steel sheet and a dent resistance and surface strain resistance that simultaneously satisfy Not only is there no disclosure about its manufacturing method,
No suggestive results are presented.
【０００４】[0004]
【発明が解決しようとする課題】本発明は、今まで、大
幅なコスト高を伴う複層鋼板だけで可能であった耐デン
ト性と耐面ひずみ性を同時に満足する冷延鋼板を安価に
製造する方法を提供するものである。DISCLOSURE OF THE INVENTION The present invention inexpensively manufactures a cold-rolled steel sheet satisfying both dent resistance and surface strain resistance, which has been possible only with a multi-layer steel sheet with a significant cost increase. It provides a way to do it.
【０００５】[0005]
【課題を解決するための手段】本発明者らは耐デント性
と耐面ひずみ性を同時に満足する冷延鋼板の製造方法を
検討し、鋼の成分と窒化条件を最適化することにより連
続焼鈍でこの種の鋼を製造できることを見いだした。本
発明の要旨とするところは、重量比でＣ ：０．００５
％以下、Ｎ ：０．０１％以下、Ｍｎ：１．５％以下、
Ｓｉ：１．０％以下、Ｐ ：０．１％以下、Ａｌ：０．
００５％以上、０．２％以下、ＴｉおよびＮｂのいずれ
か一方または双方をＣ／１２＋Ｎ／１４＋Ｓ／３２＜
０．９（Ｔｉ／４８＋Ｎｂ／９３）なる条件を満足し、
かつＴｉおよびＮｂのいずれか一方または双方を合計で
０．０２％以上含有し、必要に応じＢ：０．０００２％
以上、０．００２％以下を添加し、残部Ｆｅおよび不可
避的不純物からなる鋼を、冷延後、連続焼鈍炉内で再結
晶焼鈍をした後、６００℃以上、８００℃以下の窒化雰
囲気でＮＨ3 の濃度（％）とこの温度域での滞在時間
（秒）の積が５０以上、５００以下の条件で窒化処理を
することを特徴とする耐デント性ならびに耐面ひずみ性
に優れた深絞り用鋼板の製造方法にある。DISCLOSURE OF THE INVENTION The present inventors have investigated a method for producing a cold-rolled steel sheet satisfying both dent resistance and surface strain resistance at the same time, and by optimizing the steel composition and nitriding conditions, continuous annealing Found that it is possible to produce this type of steel. The gist of the present invention is that C: 0.005 by weight.
% Or less, N: 0.01% or less, Mn: 1.5% or less,
Si: 1.0% or less, P: 0.1% or less, Al: 0.
005% or more, 0.2% or less, one or both of Ti and Nb is C / 12 + N / 14 + S / 32 <
Satisfies the condition of 0.9 (Ti / 48 + Nb / 93),
In addition, one or both of Ti and Nb are contained in a total amount of 0.02% or more, and if necessary, B: 0.0002%.
As described above, 0.002% or less is added, and the steel consisting of the balance Fe and unavoidable impurities is cold-rolled, recrystallized and annealed in a continuous annealing furnace, and then NH in a nitriding atmosphere of 600 ° C or more and 800 ° C or less. Deep drawing with excellent dent resistance and surface strain resistance, characterized by nitriding under conditions where the product of concentration (%) of 3 and residence time (seconds) in this temperature range is 50 or more and 500 or less. It is in the method of manufacturing steel sheets for use.
【０００６】以下に、本発明について詳細に説明する。
本発明の成分の限定理由は次の通りである。Ｔｉおよび
Ｎｂのいずれか一方又は双方を０．９（Ｔｉ／４８＋Ｎ
ｂ／９３）＞Ｃ／１２＋Ｎ／１４＋Ｓ／３２なる関係を
満足し、かつＴｉおよびＮｂのいずれか一方又は双方の
添加量の和を０．０２％以上と限定したのは、鋼中のＣ
およびＮを析出物の形で固定し、固溶のＣ，Ｎを冷延時
にほとんど存在させずにスムースな結晶回転を可能にす
ることにより、その後の再結晶焼鈍で製品の深絞り性を
良好ならしめるに有利な方位である（１１１）＜１１２
＞，（５５４）＜２２５＞などの集積度の高い集合組織
を有する鋼板を得ることができること、それに、窒化時
に必要な強度の上昇が得られるためである。The present invention will be described in detail below.
The reasons for limiting the components of the present invention are as follows. One or both of Ti and Nb is 0.9 (Ti / 48 + N
b / 93)> C / 12 + N / 14 + S / 32 and the sum of the addition amounts of either or both of Ti and Nb is limited to 0.02% or more.
By fixing N and N in the form of precipitates and allowing solid crystal C and N to hardly exist during cold rolling, and enabling smooth crystal rotation, good deep drawability of the product in subsequent recrystallization annealing is achieved. It is an advantageous azimuth for training (111) <112
This is because it is possible to obtain a steel sheet having a highly integrated texture such as>, (554) <225>, and to obtain the required increase in strength during nitriding.
【０００７】一方、Ｃ：０．００５％以下、Ｎ：０．０
１％以下、Ｓ：０．０２％以下としたのはこれらの量を
越えて、Ｃ，Ｎ，Ｓを添加すると製品の加工性を損なう
のみならず上記条件式を満足せしめるに必要なＴｉある
いはＮｂの量が多くなり、不必要に製造コストを高くす
るためである。なお他の成分として、強度向上のために
通常含まれる成分即ち、Ｓｉ、Ｍｎ、Ｐの上限をそれぞ
れＳｉ：１．０％以下、Ｍｎ：１．５％以下、Ｐ：０．
１５％としたのは、これ以上に添加は加工性を劣化する
ためである。また、Ｂの添加は２次加工性を高めるの
で、必要に応じ０．０００２％以上のＢを添加すること
は効果的であるが、０．００５０％以上になると加工性
の劣化が著しくなるので、上限は０．００５０％とす
る。Ａｌは溶鋼での確実な脱酸を可能にするために少な
くとも０．００５％の添加が必要であるが、過度の添加
は加工性を劣化するので上限を０．２％とした。On the other hand, C: 0.005% or less, N: 0.0
The content of 1% or less and S: 0.02% or less means that if these amounts are exceeded and C, N, and S are added, not only the workability of the product is impaired but also Ti necessary for satisfying the above conditional expression or This is because the amount of Nb increases and the manufacturing cost unnecessarily increases. As other components, the components that are usually contained for improving strength, that is, the upper limits of Si, Mn, and P are Si: 1.0% or less, Mn: 1.5% or less, and P: 0.
The reason why it is set to 15% is that the addition thereof further deteriorates the workability. Further, since the addition of B enhances the secondary workability, it is effective to add 0.0002% or more of B as required, but if it is 0.0050% or more, the workability is significantly deteriorated. The upper limit is 0.0050%. Al needs to be added in an amount of at least 0.005% to enable reliable deoxidation in molten steel, but excessive addition deteriorates workability, so the upper limit was made 0.2%.
【０００８】次に、製造プロセスの限定について説明す
る。本発明鋼の特性は加熱条件、熱延条件に大きく依存
しないので、特に限定する必要はない。すなわち、スラ
ブを再加熱した後熱延しても、直接鋳造後熱延しても差
しつかえない。また、熱延を省略した薄鋳片でも構わな
い。冷延条件も強いて限定する必要はないが、深絞り性
の好ましい集合組織を発達させるには７０％以上の冷延
率が好ましい。再結晶焼鈍条件については、鋼板が再結
晶する前に窒化雰囲気にさらされると、再結晶が顕著に
抑制されるので、窒化雰囲気となる前に再結晶する必要
がある。Next, the limitation of the manufacturing process will be described. Since the characteristics of the steel of the present invention do not largely depend on heating conditions and hot rolling conditions, there is no particular need to limit it. That is, it does not matter whether the slab is reheated and then hot-rolled or the direct slab is hot-rolled. Further, a thin cast piece from which hot rolling is omitted may be used. The cold-rolling conditions are not particularly required to be limited, but a 70% or more cold-rolling rate is preferable in order to develop a texture with favorable deep drawability. Regarding the recrystallization annealing conditions, if the steel sheet is exposed to a nitriding atmosphere before being recrystallized, recrystallization is remarkably suppressed. Therefore, it is necessary to perform recrystallization before the nitriding atmosphere is established.
【０００９】本発明の最も重要なプロセス条件は窒化条
件で、本発明鋼を６００℃以上、８００℃以下の窒化雰
囲気でＮＨ3 の濃度（％）とこの温度域での滞在時間
（秒）の積が５０以上、５００以下の条件で窒化処理す
ることにより耐デント性と耐面ひずみ性を同時に満足す
る冷延鋼板を製造することができる。窒化温度が６００
℃以下で耐デント性と耐面ひずみ性を同時に満足する冷
延鋼板を製造することができないのは、窒化が表面近傍
だけに限られるため、必要な特性を得る窒化が実現でき
ないためと考えられる。また、８００℃以上になると逆
に拡散が速く、それが原因で必要な特性を得られないも
のと思われる。The most important process condition of the present invention is the nitriding condition. The concentration of NH 3 (%) and the residence time (seconds) in this temperature range in the nitriding atmosphere of the steel of the present invention of 600 ° C. to 800 ° C. By performing the nitriding treatment under the condition that the product is 50 or more and 500 or less, it is possible to manufacture a cold-rolled steel sheet that simultaneously satisfies dent resistance and surface strain resistance. Nitriding temperature is 600
It is thought that the reason why it is not possible to manufacture a cold-rolled steel sheet that simultaneously satisfies dent resistance and surface strain resistance at ℃ or below, because nitriding is limited only to the vicinity of the surface, nitriding to obtain the required properties cannot be realized. . On the other hand, if the temperature is 800 ° C. or higher, the diffusion is rather fast, and it is considered that the necessary characteristics cannot be obtained due to the diffusion.
【００１０】ＮＨ3 の濃度（％）とこの温度域での滞在
時間（秒）の積が５０以下で耐デント性と耐面ひずみ性
を同時に満足する冷延鋼板を製造することができない理
由は明確ではないが、必ずしも窒化が十分に進行しない
のではなく、耐デント性を高める板厚方向の窒化分布が
達成されないのが原因と思われる。一方、ＮＨ3 の濃度
（％）とこの温度域での滞在時間（秒）の積が５００以
上で耐デント性と耐面ひずみ性を同時に満足する冷延鋼
板を製造することができないのは、鋼板の降伏強度が高
くなり過ぎ、形状凍結性が劣化し、面ひずみが生じるた
めと考えられる。The reason why the product of the NH 3 concentration (%) and the residence time (second) in this temperature range is 50 or less and the dent resistance and the surface strain resistance cannot be simultaneously produced cannot be manufactured. Although not clear, it is considered that the reason is that nitriding does not always proceed sufficiently and that a nitriding distribution in the plate thickness direction that enhances dent resistance is not achieved. On the other hand, when the product of the NH 3 concentration (%) and the residence time (second) in this temperature range is 500 or more, it is impossible to manufacture a cold-rolled steel sheet satisfying both dent resistance and surface strain resistance at the same time. It is considered that the yield strength of the steel sheet becomes too high, the shape fixability deteriorates, and surface strain occurs.
【００１１】[0011]
【実施例】本発明の実施例を、比較例と共に説明する。
表１に示した成分組成を有する鋼を種々の条件で窒化処
理した。これらの条件と製品特性を表２に示す。ここで
の材料は、連続鋳造スラブを１２００℃に加熱し、約９
３０℃で仕上圧延した４ｍｍ厚の熱延板を８０％冷延
し、連続焼鈍の前半で８００℃で３０秒の再結晶焼鈍を
し、その後窒化処理をしたものである。実験１から１０
までは同じ材料を用いてプロセス条件の影響を明確にし
た。また、実験１１から２３までは鋼種の影響を明らか
にした。降伏点（ＹＰ）が２５０ＭＰａ以上になると面
ひずみが生じやすいという従来の知見に基づきＹＰ＜２
５０ＭＰａならば面ひずみが発生しないとした。また、
デント性の指標は図１に示す実験装置により鋼板に負荷
を与えた後、残った凹み量でもって表した。EXAMPLES Examples of the present invention will be described together with comparative examples.
Steels having the chemical compositions shown in Table 1 were nitrided under various conditions. Table 2 shows these conditions and product characteristics. The material here is about 9% by heating the continuous cast slab to 1200 ° C.
A 4 mm-thick hot-rolled sheet finish-rolled at 30 ° C. was cold-rolled by 80%, subjected to recrystallization annealing at 800 ° C. for 30 seconds in the first half of continuous annealing, and then subjected to nitriding treatment. Experiment 1 to 10
Up to the same material was used to clarify the effect of process conditions. Further, in Experiments 11 to 23, the influence of the steel type was clarified. Based on the conventional knowledge that surface strain easily occurs when the yield point (YP) is 250 MPa or more, YP <2
If it is 50 MPa, it is assumed that the surface strain does not occur. Also,
The index of dent property was expressed by the amount of dents remaining after a load was applied to the steel sheet by the experimental apparatus shown in FIG.
【００１２】[0012]
【表１】 [Table 1]
【００１３】[0013]
【表２】 [Table 2]
【００１４】本発明範囲の実験番号３，４，５，６，
８，１１，１２，１３，１４，１５，２２は面ひずみ指
数、デント性指数共に良好で、加工性にも優れている。
一方、実験番号１は窒化処理をしてないため、耐デント
性が劣る。実験番号２は窒化が十分行われず、十分な耐
デント性が得られなかった。実験番号７は窒化過剰のた
め耐面ひずみ性に支障をきたした。実験番号９は窒化温
度が低く、窒化が十分行なわれず、十分な耐デント性が
得られなかった。実験番号１１は逆に窒化温度が高す
ぎ、アンモニアが鋼板表面で活性な窒素と水素に分解す
る前に、雰囲気中で分解を起こし、不活性な窒素になる
量が多くなるため窒化が十分行なわれず、十分な耐デン
ト性が得られなかった。Experiment numbers 3, 4, 5, 6 within the scope of the present invention
8, 11, 12, 13, 14, 15, and 22 have good surface strain index and dent index, and are also excellent in workability.
On the other hand, Experiment No. 1 is inferior in dent resistance because it is not nitrided. In Experiment No. 2, sufficient nitriding was not performed and sufficient dent resistance was not obtained. In Experiment No. 7, surface nitriding resistance was impaired due to excessive nitriding. In Experiment No. 9, the nitriding temperature was low, the nitriding was not sufficiently performed, and sufficient dent resistance was not obtained. On the contrary, in Experiment No. 11, the nitriding temperature is too high, and the ammonia decomposes in the atmosphere before it decomposes into active nitrogen and hydrogen on the surface of the steel sheet, and the amount of inactive nitrogen increases, so nitriding is sufficiently performed. Therefore, sufficient dent resistance could not be obtained.
【００１５】実験番号１６はＣ量が本発明の範囲より多
いため、板厚全域で析出物が多く生成し、ＹＰを高める
結果となり、耐面ひずみ性を満足することができなかっ
た。実験番号１７，１８，１９はそれぞれＳｉ，Ｍｎ，
Ｐ本発明の範囲より過剰に添加されているため、窒化後
ＹＰが高くなり耐面ひずみ性を満足することができなか
った。実験番号２０は０．９（Ｔｉ／４８＋Ｎｂ／９
３）＞（Ｃ／１２＋Ｎ／１４＋Ｓ／３２の条件は満足し
ているが、Ｔｉ量が本発明の範囲以下であったため、窒
化により十分なＴｉＮが析出せず、窒化の効果が十分に
出ず、十分な耐デント性が得られなかった。In Experiment No. 16, the amount of C was larger than the range of the present invention, so a large amount of precipitates were formed over the entire plate thickness, resulting in an increase in YP, and the surface strain resistance could not be satisfied. Experiment numbers 17, 18, and 19 are Si, Mn, and
P Since Y was added in excess of the range of the present invention, YP increased after nitriding and surface strain resistance could not be satisfied. Experiment number 20 is 0.9 (Ti / 48 + Nb / 9
3)> (C / 12 + N / 14 + S / 32) is satisfied, but since the Ti amount was less than the range of the present invention, sufficient TiN was not deposited by nitriding, and the effect of nitriding was not sufficiently exerted. However, sufficient dent resistance was not obtained.
【００１６】実験番号２１は０．９（Ｔｉ／４８＋Ｎｂ
／９３）＞Ｃ／１２＋Ｎ／１４＋Ｓ／３２の条件を満足
しなかったため、窒化時に析出物を形成する窒化前の固
溶のＴｉ，Ｎｂの量が少なく、窒化の効果が十分に出
ず、十分な耐デント性が得られなかった。また、実験番
号２３ではＴｉ，Ｎｂが添加されていないため、窒化の
効果が十分に出ず、十分な耐デント性が得られなかっ
た。Experiment number 21 is 0.9 (Ti / 48 + Nb
/ 93)> C / 12 + N / 14 + S / 32 is not satisfied, the amount of solid solution Ti and Nb before nitridation that forms precipitates during nitriding is small, and the effect of nitriding is not sufficiently exerted. Dent resistance was not obtained. Further, in Experiment No. 23, since Ti and Nb were not added, the effect of nitriding was not sufficiently exerted, and sufficient dent resistance was not obtained.
【００１７】[0017]
【発明の効果】本発明によれば、今まで、複層鋼板のよ
うな大幅なコスト増なしには不可能であった耐面ひずみ
性と耐デント性を同時に満足する鋼板を、安価に製造で
き工業的に価値の高い発明である。According to the present invention, it is possible to inexpensively manufacture a steel sheet satisfying both surface strain resistance and dent resistance, which has been impossible until now without a significant increase in cost, such as a multi-layer steel sheet. It is an invention that is industrially valuable.
【図１】デント性の測定の実験方法の概要を示した説明
図である。FIG. 1 is an explanatory diagram showing an outline of an experimental method for measuring dent property.
Claims (2)
／１４＋Ｓ／３２＜０．９（Ｔｉ／４８＋Ｎｂ／９３）
なる条件を満足するＴｉ、Ｎｂのいずれか一方または双
方を合計０．０２％以上含有し、残部Ｆｅおよび不可避
的不純物からなる鋼を、冷延後、連続焼鈍炉内で再結晶
焼鈍をした後、６００℃以上、８００℃以下の温度で、
かつＮＨ3 の濃度（％）とこの温度域での滞在時間
（秒）の積が５０以上、５００以下の条件で窒化処理す
ることを特徴とする耐デント性ならびに耐面ひずみ性に
優れた深絞り用鋼板の製造方法。1. By weight ratio, C: 0.005% or less, N: 0.01% or less, Mn: 1.5% or less, Si: 1.0% or less, P: 0.1% or less, Al: 0.005% or more, 0.2% or less, C / 12 + N
/14+S/32<0.9 (Ti / 48 + Nb / 93)
The steel containing either or both of Ti and Nb satisfying the following conditions in total of 0.02% or more and the balance Fe and unavoidable impurities is cold-rolled and then recrystallized in a continuous annealing furnace. At temperatures above 600 ° C and below 800 ° C,
Also, the nitriding treatment is performed under the condition that the product of the concentration (%) of NH 3 and the residence time (second) in this temperature range is 50 or more and 500 or less, and the depth is excellent in dent resistance and surface strain resistance. Manufacturing method of steel sheet for drawing.
Ｎ／１４＋Ｓ／３２＜０．９（Ｔｉ／４８＋Ｎｂ／９
３）なる条件を満足するＴｉ、Ｎｂのいずれか一方また
は双方を合計０．０２％以上含有し、残部Ｆｅおよび不
可避的不純物からなる鋼を、冷延後、連続焼鈍炉内で再
結晶焼鈍をした後、６００℃以上、８００℃以下の窒化
雰囲気でＮＨ3 の濃度（％）とこの温度域での滞在時間
（秒）の積が５０以上、５００以下の条件で窒化処理を
することを特徴とする耐デント性ならびに耐面ひずみ性
に優れた深絞り用鋼板の製造方法。2. By weight ratio, C: 0.005% or less, N: 0.01% or less, Mn: 1.5% or less, Si: 1.0% or less, P: 0.1% or less, B: 0.0002% or more, 0.002% or less, Al: 0.005% or more, 0.2% or less, C / 12 +
N / 14 + S / 32 <0.9 (Ti / 48 + Nb / 9
3) Steel containing either or both of Ti and Nb satisfying the condition 3) in a total amount of 0.02% or more and the balance Fe and unavoidable impurities is cold rolled and then recrystallized in a continuous annealing furnace. After that, the nitriding treatment is performed under the condition that the product of the concentration (%) of NH 3 and the residence time (second) in this temperature range is 50 or more and 500 or less in a nitriding atmosphere of 600 ° C or more and 800 ° C or less. And a method for producing a deep-drawing steel sheet excellent in dent resistance and surface strain resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05149557A JP3105380B2 (en) | 1993-06-21 | 1993-06-21 | Manufacturing method of cold-rolled steel sheet for deep drawing with excellent dent resistance and surface distortion resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05149557A JP3105380B2 (en) | 1993-06-21 | 1993-06-21 | Manufacturing method of cold-rolled steel sheet for deep drawing with excellent dent resistance and surface distortion resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH073429A true JPH073429A (en) | 1995-01-06 |
| JP3105380B2 JP3105380B2 (en) | 2000-10-30 |
Family
ID=15477778
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP05149557A Expired - Fee Related JP3105380B2 (en) | 1993-06-21 | 1993-06-21 | Manufacturing method of cold-rolled steel sheet for deep drawing with excellent dent resistance and surface distortion resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3105380B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005056841A1 (en) * | 2003-12-09 | 2005-06-23 | Nippon Steel Corporation | Steel sheet for containers, and manufacturing method therefor |
| WO2005068667A1 (en) * | 2004-01-19 | 2005-07-28 | Nippon Steel Corporation | Steel sheet for use in containers and manufacturing method therefor |
| EP1806420A1 (en) * | 2004-09-09 | 2007-07-11 | Nippon Steel Corporation | Steel sheet for extremely thin container and method for production thereof |
| JP2013023694A (en) * | 2011-07-15 | 2013-02-04 | Jfe Steel Corp | Cold-rolled steel sheet excellent in shape-freezing property and production method thereof |
| JP2013151738A (en) * | 2011-12-28 | 2013-08-08 | Jfe Steel Corp | High strength thin steel plate excellent in dent resistance and method for manufacturing the same |
| WO2014057519A1 (en) * | 2012-10-11 | 2014-04-17 | Ｊｆｅスチール株式会社 | Cold-rolled steel sheet with superior shape fixability and manufacturing method therefor |
-
1993
- 1993-06-21 JP JP05149557A patent/JP3105380B2/en not_active Expired - Fee Related
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005056841A1 (en) * | 2003-12-09 | 2005-06-23 | Nippon Steel Corporation | Steel sheet for containers, and manufacturing method therefor |
| WO2005068667A1 (en) * | 2004-01-19 | 2005-07-28 | Nippon Steel Corporation | Steel sheet for use in containers and manufacturing method therefor |
| KR100851691B1 (en) * | 2004-01-19 | 2008-08-11 | 신닛뽄세이테쯔 카부시키카이샤 | Steel sheet for use in containers and manufacturing method therefor |
| EP1806420A1 (en) * | 2004-09-09 | 2007-07-11 | Nippon Steel Corporation | Steel sheet for extremely thin container and method for production thereof |
| EP1806420A4 (en) * | 2004-09-09 | 2008-04-23 | Nippon Steel Corp | Steel sheet for extremely thin container and method for production thereof |
| JP2013023694A (en) * | 2011-07-15 | 2013-02-04 | Jfe Steel Corp | Cold-rolled steel sheet excellent in shape-freezing property and production method thereof |
| JP2013151738A (en) * | 2011-12-28 | 2013-08-08 | Jfe Steel Corp | High strength thin steel plate excellent in dent resistance and method for manufacturing the same |
| WO2014057519A1 (en) * | 2012-10-11 | 2014-04-17 | Ｊｆｅスチール株式会社 | Cold-rolled steel sheet with superior shape fixability and manufacturing method therefor |
| JPWO2014057519A1 (en) * | 2012-10-11 | 2016-08-25 | Ｊｆｅスチール株式会社 | Cold-rolled steel sheet having excellent shape freezing property and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3105380B2 (en) | 2000-10-30 |
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