JP2000239784A - Cold rolled steel sheet good in deep drawability, small in plane anisotropy and excellent in ridging resistance and its production - Google Patents
Cold rolled steel sheet good in deep drawability, small in plane anisotropy and excellent in ridging resistance and its productionInfo
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- JP2000239784A JP2000239784A JP3846699A JP3846699A JP2000239784A JP 2000239784 A JP2000239784 A JP 2000239784A JP 3846699 A JP3846699 A JP 3846699A JP 3846699 A JP3846699 A JP 3846699A JP 2000239784 A JP2000239784 A JP 2000239784A
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- steel sheet
- low
- cold
- rolled
- precipitates
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車車体に代表
される絞り、張出し成形を含むプレス加工して利用され
る鋼板及びそ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 steel sheet which is used by pressing including squeezing and overhanging typified by an automobile body, and a method of manufacturing the same.
【０００２】[0002]
【従来の技術】自動車車体、建材、及び缶材などの用途
に、絞り成形や張出し成形を含むプレス成形用として用
いられる鋼板では、その機械的特性として、加工性の観
点から高い延性やランクフォード値（ｒ値）が求められ
るが、これと共に加工時のしわを抑制する効果や鋼板歩
留まりの観点から、面内異方性（△ｒ）が小さいことが
求められる。さらにこれらの材料は最終製品の外側で使
用されることが多いため、加工後の表面性状が美麗であ
ることも重要となる。2. Description of the Related Art Steel sheets used for press forming including draw forming and stretch forming for uses such as automobile bodies, building materials, and can materials have high mechanical properties such as high ductility and Rankford from the viewpoint of workability. The value (r value) is required. From the viewpoint of the effect of suppressing wrinkles during processing and the yield of the steel sheet, it is required that the in-plane anisotropy (△ r) is small. Further, since these materials are often used outside the final product, it is also important that the surface properties after processing are beautiful.
【０００３】これまでに高い延性とｒ値を有する鋼板と
して、Ｃを４０ppm 以下まで低減し、さらに固溶Ｃを低
減するためＴｉ，Ｎｂなどを添加したいわゆるＩＦ鋼が
実用化されている。高いｒ値を得るためのＴｉ，Ｎｂな
どの添加量は、例えばＴｉの場合には窒化物や硫化物に
加え炭化物を生成させ、Ｃを完全に固定する必要がある
ため、Ｔｉ*＝Ｔｉ−４８（Ｃ／１２＋Ｎ／１４＋Ｓ／
３２）などで定義されるＴｉ*が正の値であるように、
またＮｂについても固溶Ｃの低減が達せられるに十分な
量が添加される。これらＴｉ，Ｎｂの添加の目的は、Ｃ
固定と共に熱延板結晶組織の微細化の効果も狙ったもの
である。Hitherto, as a steel sheet having high ductility and r-value, a so-called IF steel in which Ti, Nb and the like are added to reduce C to 40 ppm or less and further to reduce solid solution C has been put to practical use. The amount of addition of Ti, Nb or the like for obtaining a high r value is, for example, in the case of Ti, it is necessary to generate carbide in addition to nitride and sulfide, and to completely fix C, so that Ti * = Ti− 48 (C / 12 + N / 14 + S /
32) so that Ti * defined in the above is a positive value,
Also, Nb is added in an amount sufficient to achieve a reduction in solid solution C. The purpose of the addition of Ti and Nb is as follows.
The effect of the refinement of the crystal structure of the hot-rolled sheet as well as the fixation is aimed at.
【０００４】熱延板組織の微細化が冷延、焼鈍後のｒ値
を向上きせると共に、△ｒをも小さくする効果があるこ
とは良く知られている。一方、Ｔｉ，Ｎｂの添加は合金
コストや再結晶温度が上昇することによる生産性低下、
また析出物の状態のコイル長手、幅位置による均一性を
確保することが難しく、生産歩留りの低下の原因ともな
っているため、Ｔｉ，Ｎｂの低減が望まれている。Ｔ
ｉ，Ｎｂを低減した鋼においては、熱延組織が粗大化す
ることによるｒ値低下、△ｒ増大に加え、製品板を軽加
工した際にリジングと呼ばれる表面の凹凸が発生し、製
品の美麗さを損ねることが問題となり、適用拡大の障害
となっている。It is well known that the refinement of the structure of a hot-rolled sheet improves the r-value after cold rolling and annealing, and also has the effect of reducing Δr. On the other hand, the addition of Ti and Nb reduces productivity due to an increase in alloy cost and recrystallization temperature,
In addition, it is difficult to ensure the uniformity of the state of the precipitates depending on the coil length and width position, which causes a reduction in production yield. Therefore, it is desired to reduce Ti and Nb. T
In the steel with reduced i and Nb, in addition to the reduction of r value and the increase of Δr due to the coarsening of the hot-rolled structure, surface irregularities called ridging occur when the product plate is lightly processed, and the product is beautiful. This is a problem and impedes the expansion of application.
【０００５】このような状況において、極低Ｃ鋼の熱延
組織を微細化し材質向上を図るため、熱延時の高圧下や
急速冷却を適用した技術が、特開昭６１−２０４３３５
号公報、特開昭６２−１３９８２３号公報、特開昭６２
−２２７０４３号公報などで開示されている。しかし、
熱延時の高圧下や急速冷却は、形状制御や巻取り温度制
御の精度や、設備能力との兼ね合いから、実用化に向け
ての制約が多い。[0005] Under such circumstances, in order to refine the hot-rolled microstructure of ultra-low C steel and improve the quality of the steel, a technique using high pressure and rapid cooling during hot rolling is disclosed in Japanese Patent Application Laid-Open No. 61-204335.
JP, JP-A-62-139823, JP-A-62-139823
No. 2,270,43. But,
Under high pressure and rapid cooling during hot rolling, there are many restrictions for practical use from the viewpoint of the accuracy of shape control and winding temperature control and the equipment capacity.
【０００６】一方、熱延の省エネルギーの目的から、連
続鋳造の後、加熱炉を使用せず又は温度が高い内に加熱
炉に装入する、いわゆる直送圧延又はホットチャージと
呼ばれる技術が実用化されている。極低Ｃ鋼にこれらの
技術を適用したものとしては、特開昭６２−１９２５３
８号公報、特開平７−２４２９９６号公報などがある。
このうち特開昭６２−１９２５３８号公報では、熱延組
織の微細化のため熱延圧下配分の制御が必要であり、特
開平７−２４２９９６号公報は析出物の形態制御を行う
ものであるが、通常の再加熱材と同等の特性を得るため
の技術に止まっている。On the other hand, for the purpose of energy saving in hot rolling, a technique called so-called direct-feed rolling or hot charging, in which a continuous furnace is charged into a heating furnace after continuous casting without using a heating furnace or while the temperature is high, has been put to practical use. ing. Japanese Patent Application Laid-Open No. Sho 62-19253 discloses a technique in which these techniques are applied to extremely low C steel.
8 and JP-A-7-242996.
Of these, Japanese Patent Application Laid-Open No. 62-192538 requires control of distribution under hot rolling in order to refine the hot-rolled structure, and Japanese Patent Application Laid-Open No. 7-242996 controls the morphology of precipitates. However, it is limited to techniques for obtaining characteristics equivalent to those of ordinary reheating materials.
【０００７】[0007]
【発明が解決しようとする課題】本発明は、通常のＩＦ
鋼に比しＴｉ，Ｎｂ添加量が少ない極低Ｃ鋼で問題とな
る、：ｒ値低下、：△ｒ増大、：リジング発生、
を熱延高圧下や急速冷却によらず回避するための技術
を、省エネルギーを達成しつつ提供することを目的とす
る。SUMMARY OF THE INVENTION The present invention relates to a conventional IF
Problems with ultra-low C steels, in which the amounts of Ti and Nb added are smaller than steel, are: r value decrease,: △ r increase, ridging occurs,
It is an object of the present invention to provide a technique for avoiding hot rolling under high pressure or rapid cooling while achieving energy saving.
【０００８】[0008]
【課題を解決するための手段】本発明者らは、直送圧延
時の析出物形態の変化と鋼成分との関係を検討する内、
Ｔｉ，Ｎｂ添加量が固溶Ｃ，Ｎを完全に固定しているい
わゆるＩＦ鋼より少ない鋼において、直送圧延を行うこ
とにより、熱延中に微細な析出物を形成し熱延組織の微
細化効果が発現し、さらに熱延巻取り中にこの析出物の
形態が変化し、冷延焼鈍後の材質または焼鈍中の再結
晶、粒成長挙動にはほとんど影響を及ぼさなくなること
を知見し、本発明を達成したものである。Means for Solving the Problems The present inventors studied the relationship between the change in precipitate morphology during direct rolling and the steel composition,
In a steel in which the amounts of Ti and Nb added are smaller than the so-called IF steel in which solid solution C and N are completely fixed, by performing direct rolling, fine precipitates are formed during hot rolling and the hot rolled structure is refined. The effect was developed, and the morphology of these precipitates changed during hot-rolling winding, and the material after cold-rolling annealing or recrystallization during annealing and hardly affected the grain growth behavior. The invention has been achieved.
【０００９】本発明の要旨とするところは、Ｃ，Ｔｉ，
Ｎｂ量およびＴｉ*［但しＴｉ*＝Ｔｉ−４８（Ｃ／１２
＋Ｎ／１４＋Ｓ／３２）］を特定した鋼板の熱延板また
は冷延板での、炭，窒，硫化物の平均直径および密度、
さらに平均結晶粒径を制御し、冷延鋼板の絞り性、面内
異方性、耐リジング性を向上させるものである。そのた
めの方法としては、熱延条件、冷延条件、焼鈍条件を制
御することが考えられるが、連続鋳造後８５０℃以下に
冷却することなく、または５００℃以下に冷却すること
なく加熱炉にて９００℃以上の温度域かつ３０分以上の
時間再加熱し、熱間圧延することが望ましい。The gist of the present invention is that C, Ti,
Nb amount and Ti * [where Ti * = Ti-48 (C / 12
+ N / 14 + S / 32)], the average diameter and density of carbon, nitrogen and sulfide in the hot rolled sheet or the cold rolled sheet of the steel sheet specified
Further, the average crystal grain size is controlled to improve drawability, in-plane anisotropy, and ridging resistance of the cold-rolled steel sheet. As a method for that, it is conceivable to control hot rolling conditions, cold rolling conditions, and annealing conditions. However, after continuous casting, without cooling to 850 ° C or lower, or without cooling to 500 ° C or lower, a heating furnace is used. It is desirable to perform re-heating and hot rolling in a temperature range of 900 ° C. or more and for a time of 30 minutes or more.
【００１０】[0010]
【発明の実施の形態】以下、本発明において鋼成分なら
びに製造条件を限定した理由をその作用と共に詳細に説
明する。成分の含有量は重量％である。Ｃはｒ値向上、
延性向上のためには低いことが望ましいが、Ｃ低減と共
に一般的には異方性が大きくなり、リジングが発生する
ようになる。Ｃが高い場合には異方性および耐リジング
性が問題とはならないので、対象範囲を０．００４０％
以下とする。時効性が重要な用途に対しては０．００１
７％以下とすることで、時効による不具合を回避でき
る。BEST MODE FOR CARRYING OUT THE INVENTION The reasons for limiting the steel composition and the manufacturing conditions in the present invention will be described in detail below together with the operation. The content of the components is% by weight. C is an improvement in r value,
Although it is desirable to be low for improving ductility, anisotropy generally increases with decreasing C, and ridging occurs. When C is high, anisotropy and ridging resistance are not a problem, so the target range is 0.0040%.
The following is assumed. 0.001 for applications where aging is important
By setting the content to 7% or less, problems due to aging can be avoided.
【００１１】Ｔｉは、多量に含有すればＣを固定しｒ値
が高くなると共に、熱延組織が微細化し異方性および耐
リジング性も改善され、本発明の対象とはならないの
で、０．０３％以下とする。ＮｂもＴｉと同様の理由に
より０．００５％以下とする。If Ti is contained in a large amount, it fixes C and increases the r-value, and the hot-rolled structure is refined to improve the anisotropy and ridging resistance. 03% or less. Nb is made 0.005% or less for the same reason as Ti.
【００１２】Ｔｉ*は正の十分に大きな値の場合は、窒
化物、硫化物と共に炭化物を形成すると共に、固溶Ｔｉ
が残存し、本発明らよらずともｒ値向上、熱延組織微細
化、△ｒ低減、耐リジング性向上などの良好な特性を得
ることが可能となるため、０．００５％以下とする。When Ti * is a sufficiently large positive value, carbides are formed together with nitrides and sulfides, and solid solution Ti
Remains, and good properties such as improvement of r value, refinement of hot-rolled structure, reduction of Δr, and improvement of ridging resistance can be obtained without using the present invention.
【００１３】その他の元素は特に成分限定をしないが、
Ｓ，Ｎ，Ｍｎ，Ａｌは後述する析出物形態との関連で、
またＰは組織微細化との関連で本発明の効果を得るのに
好ましい範囲が存在する。いずれも通常、プレス用冷延
鋼板で適用されている含有量である。The other elements are not particularly limited, but
S, N, Mn, and Al are related to the precipitate form described below.
P has a preferable range for obtaining the effects of the present invention in relation to the refinement of the structure. Both are the contents usually applied to cold-rolled steel sheets for press.
【００１４】Ｓは０．００１０〜０．０２００％、Ｎは
０．０００５〜０．００６０％、Ｍｎは０．０１〜１．
０％、Ａｌは０．００５〜０．１０％、Ｐは０．０５％
以下であることが望ましい。各下限は析出物の形成との
関連で、少なすぎると析出物が形成されず発明効果が小
さくなり、上限は含有量が多い場合には、本発明によら
ずとも熱延板組織が微細化し、必要特性の一部または全
部が良好となることから決定した。S is 0.0010 to 0.0200%, N is 0.0005 to 0.0060%, and Mn is 0.01 to 1.0%.
0%, Al is 0.005 to 0.10%, P is 0.05%
It is desirable that: Each lower limit is related to the formation of precipitates.If the amount is too small, no precipitates are formed and the effect of the invention is reduced.If the upper limit is large, the hot-rolled sheet structure becomes finer regardless of the present invention. Was determined because some or all of the required characteristics were good.
【００１５】本発明では、析出物の径および密度を特定
範囲に制限することが重要である。本発明鋼では窒，
硫，炭化物の種類および形態はＣ，Ｓ，Ｎ，Ｍｎ，Ｔ
ｉ，Ｎｂ，Ａｌなどの窒，硫，炭化物形成元素の含有量
によって変化する。各元素は複合析出物を形成してお
り、一つの析出物の種類および各化合物についてのサイ
ズを特定することは困難である。In the present invention, it is important to limit the diameter and density of the precipitate to a specific range. In the steel of the present invention,
The types and forms of sulfur and carbides are C, S, N, Mn, T
It changes depending on the content of elements forming nitrogen, sulfur, and carbide such as i, Nb, and Al. Each element forms a composite precipitate, and it is difficult to specify the type of one precipitate and the size of each compound.
【００１６】本発明では、ＳＰＥＥＤ法により作成され
た抽出レプリカを透過型電子顕微鏡により観察した場合
に、直径が０．００５μｍ以上の析出物について密度が
１０個／μｍ3 以下、直径が０．１０μｍ以上の析出物
の密度が０．０１０個／μｍ 3 以上であることを制限条
件とする。これらの値は実験において本発明鋼と比較鋼
の析出物を観察した結果から決定した。[0016] In the present invention, it is made by the SPEED method.
When the extracted replica is observed with a transmission electron microscope
In addition, the density of precipitates having a diameter of 0.005 μm or more
10 pieces / μmThreeHereinafter, precipitates having a diameter of 0.10 μm or more
Density of 0.010 / μm ThreeArticle that restricts
Case. These values were used in experiments to compare
Was determined from the results of observation of the precipitate.
【００１７】析出物の密度は、レプリカ作成過程におけ
る電解工程において試料表面を通電した全電荷が、Ｆｅ
の２価イオン（Ｆｅ２+ ）として鋼板が電解されるのに
消費され、電解時に残滓として残る析出物が全てレプリ
カ上に補足されるとして計算した。本発明者らは、通常
のレプリカ作成においては試料表面積において１０Ｃ
（クーロン）／ｃｍ2 の電気量で電解を行うので、試料
表面から３．７μｍの厚さ内にある析出物がレプリカ上
で観察される。なお、本発明鋼で観察される析出物は主
としてＭｎＳで、これにＴｉの炭，窒，硫化物およびＡ
ｌＮが単独または複合で析出している。[0017] The density of the precipitate is determined by the fact that the total electric charge applied to the sample surface in the electrolysis step in the replica making process is Fe
Is calculated as the divalent ion (Fe 2 + ) of the steel sheet consumed during the electrolysis of the steel sheet, and the precipitates remaining as residues during the electrolysis are all captured on the replica. The present inventors have found that a 10 C
Since the electrolysis is performed with an electric quantity of (coulomb) / cm 2 , a precipitate within a thickness of 3.7 μm from the sample surface is observed on the replica. The precipitates observed in the steel of the present invention are mainly MnS, which is composed of carbon, nitride, sulfide and A of Ti.
1N is precipitated alone or in combination.
【００１８】析出物のサイズおよび密度が上記の範囲の
場合に本発明の効果が得られるメカニズムは明確ではな
いが、本発明鋼と比較鋼の析出量を析出物サイズ分布と
各サイズの析出物の密度から計算すると、比較鋼の方が
析出量が少ない傾向があることから、粒成長および再結
晶の駆動力となる加工歪と、抑止力となる析出物として
析出しきれていないＭｎ，Ｔｉ，Ｓなどによる solute
drag効果の釣合によると推定できる。The mechanism by which the effect of the present invention is obtained when the size and density of the precipitates are in the above ranges is not clear, but the precipitation amount of the steel of the present invention and the comparative steel is determined by the precipitate size distribution and the precipitate of each size. When calculated from the density of the comparative steel, since the amount of precipitation tends to be smaller in the comparative steel, Mn and Ti which have not been fully precipitated as precipitates serving as driving forces for grain growth and recrystallization and precipitates serving as deterrents are obtained. Solute by S, S, etc.
It can be estimated that the drag effect is balanced.
【００１９】すなわち、冷延板または熱延板時点での析
出物が上記のように制御された鋼板においては、（熱延
での再結晶および粒成長の駆動力）＜（ solute drag効
果）であるため、熱延組織の微細化が達成され、（冷延
後焼鈍での再結晶および粒成長の駆動力）＞（ solute
drag効果）であるため、冷延後焼鈍での再結晶不足や粒
成長不足による材質劣化が起き難くなるものと考えられ
る。That is, in a steel sheet in which precipitates at the time of a cold rolled sheet or a hot rolled sheet are controlled as described above, (driving force for recrystallization and grain growth in hot rolling) <(solute drag effect). Therefore, the microstructure of the hot-rolled structure is achieved, and the driving force for recrystallization and grain growth in annealing after cold rolling >> (solute
Therefore, it is considered that material deterioration due to insufficient recrystallization or insufficient grain growth during annealing after cold rolling hardly occurs.
【００２０】ここで上の２つの式が成立するには、（冷
延後焼鈍での再結晶および粒成長の駆動力）＞（熱延で
の再結晶およひ粒成長の駆動力）であることが必要であ
るが、一般には低温で歪が付与される冷間圧延の方が歪
の残存、蓄積が大きく、再結晶や粒成長の駆動力は大き
くなると推測されるので、上記のメカニズムが働いてい
る可能性は十分である。Here, to satisfy the above two equations, (driving force for recrystallization and grain growth in annealing after cold rolling)> (driving force for recrystallization and grain growth in hot rolling). Although it is necessary, it is generally assumed that cold rolling, in which strain is imparted at a low temperature, has higher residual and accumulated strain and a larger driving force for recrystallization and grain growth, so the mechanism described above is used. There is a good chance that is working.
【００２１】また、たとえ（冷延後焼鈍での再結晶およ
び粒成長の駆動力）と（熱延での再結晶および粒成長の
駆動力）がほぼ同等であるとしても、熱延巻取り工程ま
たは焼鈍工程前半において析出が進行し、（冷延後焼鈍
中の solute drag効果）＜（熱延中の solute drag効
果）となっている可能性も指摘できる。また、熱延中の
再結晶、粒成長は概略γ相中での現象であり、一方、冷
延後焼鈍中の再結晶、粒成長は概略α相中での現象であ
ることも考慮する必要がある。Even if (the driving force for recrystallization and grain growth in annealing after cold rolling) and (the driving force for recrystallization and grain growth in hot rolling) are almost equal, the hot rolling and winding step Alternatively, it can be pointed out that the precipitation proceeds in the first half of the annealing step, and that (the solute drag effect during annealing after cold rolling) <(the solute drag effect during hot rolling). It is also necessary to consider that recrystallization and grain growth during hot rolling are approximately in the γ phase, while recrystallization and grain growth during annealing after cold rolling are approximately in the α phase. There is.
【００２２】さらに、冷延鋼板の素材となる熱延鋼板の
結晶粒径については、５０μｍ以下とすることが好まし
い。熱延板の粒径が５０μｍ超の場合にはｒ値、△ｒ、
リジングとも特性が劣化することがある。冷延圧下率
は、６０〜９０％とする。６０％未満では熱延鋼板との
比較で生産コストが上昇するため実用的でないことと、
９０％超では本発明によらずともｒ値、△ｒ、耐リジン
グ性の改善が可能となるからである。Further, the crystal grain size of the hot-rolled steel sheet used as the material of the cold-rolled steel sheet is preferably set to 50 μm or less. When the particle size of the hot-rolled sheet exceeds 50 μm, the r value, Δr,
The characteristics of both ridgings may deteriorate. The cold rolling reduction is 60 to 90%. If it is less than 60%, it is impractical because the production cost increases compared to hot rolled steel sheet,
If the content exceeds 90%, the r value, Δr, and ridging resistance can be improved without using the present invention.
【００２３】冷延後に焼鈍するが、この温度は再結晶温
度以上であれば良く、特に限定しない。一般には直送圧
延材では析出物が微細化し焼鈍中の再結晶、粒成長を阻
害するため、通常のスラブ再加熱材より高い焼鈍温度が
必要、または同じ焼鈍温度なら材質の劣化が問題となる
が、本発明鋼では再結晶温度ならびに粒成長性はスラブ
再加熱材と同等であるため、低い焼鈍温度の適用が可能
となる。Annealing is performed after cold rolling, and the temperature is not particularly limited as long as it is equal to or higher than the recrystallization temperature. In general, in direct-rolled materials, precipitates become finer and recrystallization during annealing, which hinders grain growth.Therefore, a higher annealing temperature is required than a normal slab reheated material, or if the same annealing temperature, deterioration of the material becomes a problem. On the other hand, in the steel of the present invention, since the recrystallization temperature and the grain growth are the same as those of the slab reheated material, a low annealing temperature can be applied.
【００２４】通常、本発明鋼板は表面処理鋼板用の原板
として使用されるが、表面処理により本発明の効果はな
んら損なわれるものではない。缶用表面処理としては通
常、錫、クロム（ティンフリー）などが、自動車、建材
用表面処理としては、亜鉛、鉛、アルミ、ニッケル、ク
ロムなどが施される。また、近年使用されるようになっ
ている有機皮膜を貼ったラミネート鋼板用の原板として
も、本発明の効果を損なうことなく使用できる。Usually, the steel sheet of the present invention is used as an original sheet for a surface-treated steel sheet, but the surface treatment does not impair the effects of the present invention at all. Usually, tin and chrome (tin-free) are applied as surface treatments for cans, and zinc, lead, aluminum, nickel, chromium and the like are applied as surface treatments for automobiles and building materials. Further, it can also be used as a base plate for a laminated steel sheet to which an organic film, which has been used in recent years, is attached without impairing the effects of the present invention.
【００２５】[0025]
【実施例】表１に示す各成分の鋼（残部は実質的にＦｅ
(不可避的不純物を含む) ）について、通常の熱間圧延
条件により表２のような熱延鋼板を得、冷間圧延、焼鈍
した鋼板について材質を評価した。耐リジング性の評価
はＬおよびＣ方向に１５％の伸び率で引張加工を行った
試験片の表面粗度（Ｒａ）を測定し、大きい方の値で評
価した。その結果を表３に示す。表３から明らかなよう
に、本発明の範囲内で製造されたものは良好な特性が得
られている。また，成分が本発明範囲外である成分ｃ，
ｄ鋼では、通常のスラブ再加熱法においても良好な特性
が得られるため、本発明対象外としている。EXAMPLE Steel of each component shown in Table 1 (substantially Fe
(Including inevitable impurities)), hot rolled steel sheets as shown in Table 2 were obtained under normal hot rolling conditions, and the materials of the cold rolled and annealed steel sheets were evaluated. The ridging resistance was evaluated by measuring the surface roughness (Ra) of a test piece subjected to tensile processing in the L and C directions at an elongation of 15% and evaluating the larger value. Table 3 shows the results. As is evident from Table 3, those manufactured within the scope of the present invention have good properties. Component c, whose component is outside the scope of the present invention,
The d steel is excluded from the scope of the present invention because good characteristics can be obtained even by a normal slab reheating method.
【００２６】[0026]
【表１】 [Table 1]
【００２７】[0027]
【表２】 [Table 2]
【００２８】[0028]
【表３】 [Table 3]
【００２９】[0029]
【発明の効果】以上述べたごとく本発明によれば、延性
が良好で再結晶温度が低い低Ｔｉ，低Ｎｂ極低Ｃ鋼板に
高ｒ値、低△ｒ、良好な耐リジング性を付与し、かつ低
コスト・省エネルギープロセスで製造することができ
る。As described above, according to the present invention, a low Ti, low Nb extremely low C steel sheet having good ductility and low recrystallization temperature is provided with a high r value, a low Δr, and a good ridging resistance. , And can be manufactured by a low cost and energy saving process.
フロントページの続き Ｆターム(参考） 4K037 EA01 EA04 EA15 EA18 EA19 EA23 EA25 EA31 EB01 EB02 EB06 EB08 EC01 EC04 FA02 FA05 FA06 GA04 GA05 HA04 HA06 JA06 Continued on the front page F term (reference) 4K037 EA01 EA04 EA15 EA18 EA19 EA23 EA25 EA31 EB01 EB02 EB06 EB08 EC01 EC04 FA02 FA05 FA06 GA04 GA05 HA04 HA06 JA06
Claims (6)
２＋Ｎ／１４＋Ｓ／３２）］ なる成分を含有し、板厚０．４ｍｍ以上であることを特
徴とする深絞り性が良好で面内異方性が小さく、耐リジ
ング性に優れる冷延鋼板。1. In weight%, C <0.0040%, Ti <0.030%, Nb <0.005%, Ti * <0.005% [where Ti * = Ti−48 (C / 1
2 + N / 14 + S / 32)] A cold-rolled steel sheet having good deep drawability, low in-plane anisotropy, and excellent ridging resistance, characterized by having a thickness of 0.4 mm or more.
が１０個／μｍ3 以下、直径０．１０μｍ以上の析出物
の密度が０．０１０個／μｍ3 以上であることを特徴と
する請求項１記載の深絞り性が良好で面内異方性が小さ
く、耐リジング性に優れる冷延鋼板。2. The density of precipitates having a diameter of 0.005 μm or more is 10 / μm 3 or less, and the density of precipitates having a diameter of 0.10 μm or more is 0.010 / μm 3 or more. Item 1. A cold-rolled steel sheet according to Item 1, which has good deep drawability, low in-plane anisotropy, and excellent ridging resistance.
２＋Ｎ／１４＋Ｓ／３２）］ を含有する鋼を熱延し、６０〜９０％の圧下率の冷間圧
延を施し、その後焼鈍して、直径０．００５μｍ以上の
析出物の密度が１０個／μｍ3 以下、直径０．１０μｍ
以上の析出物の密度が０．０１０個／μｍ3 以上とする
ことを特徴とする深絞り性が良好で面内異方性が小さ
く、耐リジング性に優れる冷延鋼板の製造方法。3. In% by weight, C <0.0040%, Ti <0.030%, Nb <0.005%, Ti * <0.005% [where Ti * = Ti−48 (C / 1
2 + N / 14 + S / 32)] is hot-rolled, cold-rolled at a rolling reduction of 60 to 90%, and then annealed, and the density of precipitates having a diameter of 0.005 μm or more is 10 grains / μm. 3 or less, diameter 0.10μm
A method for producing a cold-rolled steel sheet having good deep drawability, low in-plane anisotropy, and excellent ridging resistance, wherein the density of the precipitates is 0.010 / μm 3 or more.
て製造した鋼片を用いることを特徴とする請求項３記載
の深絞り性が良好で面内異方性が小さく、耐リジング性
に優れる冷延鋼板の製造方法。4. A steel slab manufactured by continuous casting is used as the steel before hot rolling, wherein the steel has good deep drawability, low in-plane anisotropy, and low ridging resistance. Excellent cold rolled steel sheet manufacturing method.
後、８５０℃以下に冷却することなく熱間圧延すること
を特徴とする請求項３又は４記載の深絞り性が良好で面
内異方性が小さく、耐リジング性に優れる冷延鋼板の製
造方法。5. The steel sheet obtained by continuous casting is hot-rolled without being cooled to 850 ° C. or lower after casting, and has a good deep drawability and an in-plane irregularity. A method for producing a cold-rolled steel sheet with low anisotropy and excellent ridging resistance.
後、５００℃以下に冷却することなく、加熱炉で９００
℃以上・３０分以上の再加熱を行い、熱間圧延すること
を特徴とする請求項３又は４記載の深絞り性が良好で面
内異方性が小さく、耐リジング性に優れる冷延鋼板の製
造方法。6. A steel slab obtained by continuous casting is cast in a heating furnace without being cooled to 500 ° C. or less after casting.
The cold-rolled steel sheet according to claim 3 or 4, wherein the cold-rolled steel sheet has good deep drawability, small in-plane anisotropy, and excellent ridging resistance. Manufacturing method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03846699A JP4283365B2 (en) | 1999-02-17 | 1999-02-17 | Method for producing cold-rolled steel sheet with good deep drawability, small in-plane anisotropy and excellent ridging resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03846699A JP4283365B2 (en) | 1999-02-17 | 1999-02-17 | Method for producing cold-rolled steel sheet with good deep drawability, small in-plane anisotropy and excellent ridging resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2000239784A true JP2000239784A (en) | 2000-09-05 |
| JP4283365B2 JP4283365B2 (en) | 2009-06-24 |
Family
ID=12526035
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP03846699A Expired - Fee Related JP4283365B2 (en) | 1999-02-17 | 1999-02-17 | Method for producing cold-rolled steel sheet with good deep drawability, small in-plane anisotropy and excellent ridging resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4283365B2 (en) |
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1999
- 1999-02-17 JP JP03846699A patent/JP4283365B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JP4283365B2 (en) | 2009-06-24 |
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