JP4555693B2 - High-strength cold-rolled steel sheet excellent in deep drawability and manufacturing method thereof - Google Patents
High-strength cold-rolled steel sheet excellent in deep drawability and manufacturing method thereof Download PDFInfo
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Description
本発明は、主に自動車のパネル類、足廻り、メンバーフレームなどの部品に用いられる鋼板およびその製造方法に関するものである。本発明の鋼板は表面処理をしない冷延鋼板と、防錆の目的で溶融亜鉛めっき、電気めっきなどの表面処理を施しためっき鋼板の両方を含む。また、めっきの種類としては純亜鉛、主成分が亜鉛である合金、さらにはＡｌやＡｌ−Ｍｇを主体としたものも含む。 The present invention relates to a steel plate used mainly for parts such as automobile panels, undercarriages, and member frames, and a method for manufacturing the same. The steel sheet of the present invention includes both cold-rolled steel sheets that are not subjected to surface treatment and plated steel sheets that have been subjected to surface treatment such as hot dip galvanizing and electroplating for the purpose of rust prevention. In addition, the types of plating include pure zinc, alloys whose main component is zinc, and those mainly composed of Al or Al-Mg.
近年の自動車軽量化の動きに伴い、高強度鋼板の自動車部材への適用ニーズが高まっている。これは高強度化することで板厚減少による軽量化や衝突時の安全性向上が期待できるためである。しかしながら、自動車の車体用部品の多くはプレス加工により成形されるために使用される高強度鋼板には優れたプレス成形性が要求される。成形性、特に深絞り性が優れた鋼板を得るためにはＣ量を著しく低減する事が有効であることは良く知られている。 With the recent trend of reducing the weight of automobiles, there is an increasing need for application of high-strength steel sheets to automobile members. This is because by increasing the strength, it is possible to expect weight reduction by reducing the plate thickness and safety improvement at the time of collision. However, many press parts for automobile body parts are required to have excellent press formability because they are formed by press working. It is well known that it is effective to significantly reduce the amount of C in order to obtain a steel sheet having excellent formability, particularly deep drawability.
そこで高強度鋼の深絞り性向上のために、特開昭５６−１３９６５４号公報（特許文献１）に開示されているように、Ｃ量を著しく減じた極低炭素鋼にＳｉ，Ｍｎ，Ｐなどを添加して強化する鋼板が多く開発された。しかしながら、Ｃ量を低減するためには製鋼工程で真空脱ガスを行わなければならず、製造工程でＣＯ2 を多量に発生することになり、コストの観点からも地球環境保全の観点からも最良とはいえない。また、Ｃ量が低いと残留γ鋼のような強度延性バランスに優れた複合組織鋼を作ることが出来ない。 Therefore, in order to improve the deep drawability of high strength steel, as disclosed in JP-A-56-139654 (Patent Document 1), an ultra-low carbon steel with a significantly reduced amount of C is added to Si, Mn, P Many steel sheets have been developed that are reinforced with the addition of the above. However, in order to reduce the amount of C, vacuum degassing must be performed in the steel making process, and a large amount of CO 2 is generated in the manufacturing process, which is the best from the viewpoint of cost and global environmental conservation. That's not true. Moreover, when the amount of C is low, it is not possible to make a composite structure steel having an excellent balance of strength and ductility such as residual γ steel.
これに対し、Ｃ量が比較的高く、かつ深絞り性の良好な鋼板についても、特公昭５７−４７７４６号公報（特許文献２）、特公平２−２０６９５号公報（特許文献３）などに開示されている。しかしながら、これらは箱焼鈍が前提となっており、連続焼鈍に比較すると生産性に劣る。また、高温昇温、急速冷却が困難なことから残留オーステナイト相やマルテンサイト相を得ることが難しく、組織強化が活用しにくい。 On the other hand, steel sheets with a relatively high C content and good deep drawability are disclosed in Japanese Patent Publication No. 57-47746 (Patent Document 2), Japanese Patent Publication No. 2-20695 (Patent Document 3), and the like. Has been. However, these are premised on box annealing, and are inferior in productivity as compared with continuous annealing. Moreover, since it is difficult to raise the temperature and rapidly cool, it is difficult to obtain a retained austenite phase or a martensite phase, and it is difficult to utilize the strengthening of the structure.
この問題を解決するために、例えば特公昭５５−１０６５０号公報（特許文献４）や特開昭５５−１００９３４号公報（特許文献５）では箱焼鈍の後に連続焼鈍を行うような技術が開示されているが、生産性の問題は回避することが出来ない。また、特開２００３−６４４４３号公報（特許文献６）、特開２００３−１９３１９１号公報（特許文献７）、特開２００３−３２１７３３号公報（特許文献８）、特開２００３−４２６４３号公報（特許文献９）には連続焼鈍工程で深絞り性に優れた高強度冷延鋼板を製造する技術が開示されているが、いずれも熱延板の金属組織や固溶Ｃ量を規定することで冷延中の｛１１１｝方位の発達を促すことを目的としており、本発明とはまったく異なるものである。 In order to solve this problem, for example, Japanese Patent Publication No. 55-10650 (Patent Document 4) and Japanese Patent Application Laid-Open No. 55-1000093 (Patent Document 5) disclose a technique of performing continuous annealing after box annealing. However, productivity problems cannot be avoided. JP 2003-64443 A (Patent Document 6), JP 2003-193191 A (Patent Document 7), JP 2003-321733 A (Patent Document 8), JP 2003-42643 A (Patent Document 6). Reference 9) discloses a technique for producing a high-strength cold-rolled steel sheet excellent in deep drawability in a continuous annealing process. The purpose is to promote the development of the {111} orientation, which is completely different from the present invention.
本発明はＣ量の比較的多い鋼において成形性、特に深絞り性の良好な高強度鋼板を、連続焼鈍工程を前提とした通常の製造ラインにおいて製造し、提供することを目的とする。 An object of the present invention is to manufacture and provide a high strength steel plate having good formability, particularly deep drawability in a steel having a relatively large amount of C, in a normal production line based on a continuous annealing process.
本発明者らが上記のような課題を解決すべく鋭意検討を進めたところ、熱延板の集合組織、冷延率、焼鈍時の加熱速度を制御することによってＣ量が比較的多くても深絞り性の良好な鋼板を連続焼鈍で製造することが可能であることを見出した。すなわち、Ｎｂ，Ｍｏ，Ｔｉ，Ｍｎ，Ｂ等の成分、及び熱延条件を最適化することで、熱延板中にｒ値を高める方位である｛３３２｝＜１１３＞が極めて高くなり、かつｒ値を下げる方位である｛１００｝＜０１１＞方位の強度が低下することを見出したものである。そして、この熱延板集合組織を冷延・焼鈍後まで保存することで高い深絞り性を確保するという、今までにない考え方によって高深絞り性鋼板を製造するものである。 When the present inventors have intensively studied to solve the above problems, even if the amount of C is relatively large by controlling the texture of the hot rolled sheet, the cold rolling rate, and the heating rate during annealing. It has been found that a steel sheet with good deep drawability can be produced by continuous annealing. That is, by optimizing components such as Nb, Mo, Ti, Mn, B, and hot rolling conditions, {332} <113>, which is an orientation for increasing the r value in the hot rolled sheet, becomes extremely high, and It has been found that the strength of the {100} <011> orientation, which is the orientation that lowers the r value, decreases. Then, a high deep drawability steel sheet is manufactured by an unprecedented concept of ensuring high deep drawability by preserving this hot rolled sheet texture until after cold rolling and annealing.
本発明の要旨とするところは
（１）質量％で、Ｃ：０．０１〜０．３％、Ｓｉ：２．５％以下、Ｍｎ：０．１〜３．０％、Ｐ：０．１５％以下、Ｓ：０．０１５％以下、Ｍｏ：０．１〜１．５％、Ｂ：０．０００６〜０．０１％、Ａｌ：０．１５％以下、Ｎｂ：０．０１〜０．２０％、Ｎ：０．０１％以下、Ｔｉ：４８／１４×Ｎ（質量％）以上、０．２％以下を含有し、残部鉄及び不可避的不純物からなり、板厚１／２層における｛３３２｝＜１１３＞の極密度が４．５以上でかつ｛１００｝＜０１１＞の極密度が３以下、更に圧延方向と４５度方向と幅方向のｒ値の最小値が１．０以上で、かつ圧延方向と４５度方向と幅方向の平均ｒ値が１．３以上であることを特徴とする深絞り性に優れた高強度冷延鋼板。
The gist of the present invention is (1)% by mass, C: 0.01 to 0.3%, Si: 2.5% or less, Mn: 0.1 to 3.0%, P: 0.15. %: S: 0.015% or less, Mo: 0.1-1.5%, B: 0.0006-0.01%, Al: 0.15% or less, Nb: 0.01-0.20 %, N: 0.01% or less, Ti: 48/14 × N (mass%) or more and 0.2% or less, consisting of the balance iron and unavoidable impurities, {332 in thickness 1/2 layer } <113> has a pole density of 4.5 or more and {100} <011> has a pole density of 3 or less, and the minimum r value in the rolling direction, 45 degree direction and width direction is 1.0 or more, A high-strength cold-rolled steel sheet excellent in deep drawability, characterized in that the average r value in the rolling direction, 45 ° direction and width direction is 1.3 or more.
（２）板厚１／８層における｛１１０｝＜２２３＞及び／又は｛１１０｝＜１１１＞の極密度が４以下であることを特徴とする前記（１）に記載の深絞り性に優れた高強度冷延鋼板。
（３）Ｃａ：０．０００５〜０．０１質量％を含むことを特徴とする前記（１）又は（２）に記載の深絞り性に優れた高強度冷延鋼板。
(2) The deep density of {110} <223> and / or {110} <111> in the plate thickness 1/8 layer is excellent in deep drawability as described in (1) above, which is 4 or less High strength cold rolled steel sheet.
(3) The high-strength cold-rolled steel sheet having excellent deep drawability as described in (1) or (2) above, containing Ca: 0.0005 to 0.01% by mass.
（４）Ｓｎ，Ｃｏ，Ｚｎ，Ｗ，Ｚｒ，Ｖ，Ｍｇ，Ｒｅｍの１種又は２種以上を合計で０．００１〜１．０質量％含むことを特徴とする前記（１）〜（３）のいずれか１項に記載の深絞り性に優れた高強度冷延鋼板。
（５）Ｎｉ，Ｃｕ，Ｃｒの１種又は２種以上を合計で０．００１〜４．０質量％含むことを特徴とする前記（１）〜（４）のいずれか１項に記載の深絞り性に優れた高強度冷延鋼板。
(4) The above (1) to (3) characterized by containing 0.001 to 1.0 mass% in total of one or more of Sn, Co, Zn, W, Zr, V, Mg, and Rem. The high-strength cold-rolled steel sheet excellent in deep drawability according to any one of items 1).
(5) The depth according to any one of (1) to (4) above, wherein 0.001 to 4.0 mass% in total of one or more of Ni, Cu, and Cr is included. A high-strength cold-rolled steel sheet with excellent drawability.
（６）前記（１）および（３）〜（５）のいずれか１項に記載の化学成分を有するスラブを１１００℃以上の温度に加熱し、熱間圧延をする際、（１）式で計算される有効ひずみ量ε* が０．４以上、かつ圧下率の合計が５０％以上となるように圧延を行い、Ａｒ3 変態点以上９００℃以下の温度で熱間圧延を終了した後、７００℃以下で巻取り、圧下率３０％超、７０％以下の冷間圧延を施した後、３〜５０℃／ｓの加熱速度で最高到達温度５００℃以上９５０℃以下の温度範囲となるように焼鈍することを特徴とする（１）〜（５）の何れか１項に記載の深絞り性に優れた高強度冷延鋼板の製造方法。 (6) When the slab having the chemical component according to any one of (1) and (3) to (5) is heated to a temperature of 1100 ° C. or higher and hot rolled, Rolling is performed so that the calculated effective strain amount ε * is 0.4 or more and the total reduction ratio is 50% or more, and after the hot rolling is completed at a temperature of Ar 3 transformation point or more and 900 ° C. or less, After winding at 700 ° C. or less, cold rolling with a rolling reduction of more than 30% and 70% or less, at a heating rate of 3 to 50 ° C./s, a maximum temperature of 500 ° C. to 950 ° C. is reached. The method for producing a high-strength cold-rolled steel sheet excellent in deep drawability according to any one of (1) to (5), wherein the steel sheet is annealed.
τｉ＝８．４６×１０-9・ｅｘｐ｛４３８００／Ｒ／Ｔｉ｝
τi = 8.46 × 10 −9 · exp {43800 / R / Ti}
（７）熱間圧延において、少なくとも１パス以上を摩擦係数が０．２以下となるように仕上げ圧延することを特徴とする前記（６）に記載の深絞り性に優れた高強度冷延鋼板の製造方法。
（８）焼鈍した後、溶融亜鉛めっきを施すことを特徴とする前記（６）又は（７）記載の溶融亜鉛めっき鋼板の製造方法。
（９）溶融亜鉛めっきを施した後、４５０〜６００℃までの温度範囲で１０ｓ以上の熱処理を行うことを特徴とする前記（８）記載の合金化溶融亜鉛めっき鋼板の製造方法にある。
(7) In hot rolling, at least one pass or more is finish-rolled so that the friction coefficient is 0.2 or less, and the high-strength cold-rolled steel sheet having excellent deep drawability as described in (6) above Manufacturing method.
(8) The method for producing a hot-dip galvanized steel sheet according to (6) or (7), wherein hot-dip galvanizing is performed after annealing.
(9) In the method for producing an galvannealed steel sheet according to (8), heat treatment is performed for 10 s or more in a temperature range from 450 to 600 ° C. after galvanizing.
以上述べたように、本発明によれば成形性に優れた高強度冷延鋼板を製造することができるために、従来高強度鋼では成形が難しかった部材への適用が可能になり、例えば自動車の軽量化による燃費向上、それに伴うＣＯ2 排出量削減等を通して地球環境保全に貢献するものである。 As described above, according to the present invention, a high-strength cold-rolled steel sheet having excellent formability can be produced. Therefore, it can be applied to members that have been difficult to form with conventional high-strength steel. This contributes to the conservation of the global environment through the improvement of fuel consumption and the reduction of CO 2 emissions.
ここに、本発明において鋼組成および製造条件を上述のように限定する理由についてさらに説明する。
Ｃは、安価に引張強度を増加させる元素であるので、積極的に添加する。その添加量は狙いとする強度レベルに応じて変化するが、０．０１％未満にすることはコストアップとなるだけでなく、組織制御の自由度が下がることからその下限を０．０１％とする。この観点からは０．０２％とすることが望ましい。一方、Ｃ量が０．３％を超えると成形性の劣化を招いたり、溶接性を損なったりするのでこれを上限とする。
Here, the reason why the steel composition and production conditions are limited as described above in the present invention will be further described.
Since C is an element that increases the tensile strength at a low cost, it is positively added. The amount of addition varies depending on the target strength level, but if it is less than 0.01%, not only will the cost be increased, but the degree of freedom in tissue control will be reduced, so the lower limit is 0.01%. To do. From this viewpoint, the content is preferably 0.02%. On the other hand, if the amount of C exceeds 0.3%, the formability is deteriorated or the weldability is impaired.
Ｓｉは、固溶体強化元素として強度を増加させる働きがあることの他、マルテンサイトやベイナイトさらには残留γ等を含む組織を得るためにも有効であり、その添加量は狙いとする強度レベルに応じて変化するが、添加量が２．５％超となるとプレス成形性が劣悪となったり、化成処理性の低下を招いたりするのでこれを上限とする。
溶融亜鉛めっきを施す場合には、めっき密着性の低下、合金化反応の遅延による生産性の低下などの問題が生ずるので１．２％以下とすることが好ましい。下限は特に設けないが、０．００１％以下とするのは製造コストが高くなるのでこれが実質的な下限である。
Si has a function of increasing strength as a solid solution strengthening element, and is also effective for obtaining a structure containing martensite, bainite, and residual γ. The amount of addition depends on the target strength level. However, if the added amount exceeds 2.5%, the press formability is deteriorated or the chemical conversion treatment property is deteriorated.
When hot dip galvanizing is performed, problems such as a decrease in plating adhesion and a decrease in productivity due to a delay in the alloying reaction occur, so 1.2% or less is preferable. Although there is no particular lower limit, setting it to 0.001% or less is a practical lower limit because the manufacturing cost increases.
Ｍｎは、γ相を安定化し、γ域を低温まで拡張するのでγ域低温圧延を容易にすることから積極的に添加する。ただし、３．０％を超えて添加すると強度が高くなりすぎて延性が低下したり、亜鉛めっきの密着性が阻害されたりするのでこれを上限とする。好ましくは２．０％以下とする。Ｍｎが０．１％未満になると強度不足になると共に、固溶Ｓ起因の熱間圧延割れを誘発することから０．１％を下限とする。強度確保の観点からは０．３％以上添加することが望ましい。 Mn is positively added because it stabilizes the γ phase and expands the γ region to a low temperature, facilitating γ region low temperature rolling. However, if added over 3.0%, the strength becomes too high and the ductility is lowered or the adhesion of galvanizing is inhibited, so this is the upper limit. Preferably it is 2.0% or less. If Mn is less than 0.1%, the strength is insufficient, and hot rolling cracks due to solute S are induced, so 0.1% is made the lower limit. From the viewpoint of securing strength, it is desirable to add 0.3% or more.
Ｐは、不純物であるが、Ｓｉと同様に安価に強度を高める元素として知られており強度を増加する必要がある場合にはさらに積極的に添加する。また、Ｐは熱延組織を微細にし、加工性を向上する効果も有する。ただし、添加量が０．１５％を超えると、スポット溶接後の疲労強度が劣悪となったり、降伏強度が増加し過ぎたりしてプレス時に面形状不良を引き起こす。さらに、連続溶融亜鉛めっき時に合金化反応が極めて遅くなり、生産性が低下する。また、２次加工性も劣化する。したがって、その上限値を０．１５％とする。 Although P is an impurity, it is known as an element that increases the strength at a low cost similarly to Si, and is more actively added when it is necessary to increase the strength. P also has the effect of making the hot-rolled structure fine and improving workability. However, if the addition amount exceeds 0.15%, the fatigue strength after spot welding becomes poor, or the yield strength increases excessively, causing surface shape defects during pressing. Furthermore, the alloying reaction becomes extremely slow during continuous hot dip galvanizing, and productivity is lowered. Also, the secondary workability is deteriorated. Therefore, the upper limit is set to 0.15%.
Ｓは、不純物であり少ないほど好ましく、０．０１５％超では熱間割れの原因となったり、加工性を劣化させるので、これを上限とする。
Ｍｏ，ＮｂおよびＢは本発明において重要である。これらの元素の添加によって初めて圧延方向のヤング率を高めることが可能となる。この理由は必ずしも明らかではないが、Ｍｏ、Ｎｂ，Ｂの複合添加の効果によって、熱延中の再結晶が抑制され、γ相の加工集合組織が先鋭化することで、加工γからの変態集合組織であり、ｒ値に有利な｛３３２｝＜１１３＞方位が先鋭化すると考えられる。
S is preferably as small as possible, and if it exceeds 0.015%, it causes hot cracking and deteriorates workability, so this is the upper limit.
Mo, Nb and B are important in the present invention. Only when these elements are added can the Young's modulus in the rolling direction be increased. The reason for this is not necessarily clear, but the effect of combined addition of Mo, Nb, and B suppresses recrystallization during hot rolling and sharpens the working texture of the γ phase. It is considered that the {332} <113> orientation which is a texture and advantageous for the r value is sharpened.
また、その後の焼鈍中の再結晶も抑制されることから、熱延での集合組織を破壊することなく焼鈍後まで持ちきたすことにも効果を発揮する。加えてこれらの元素はγ→α変態時の焼入れ性を向上させることから、二相域又はγ域単相で焼鈍を行って、α→γ→α変態を経ても集合組織が崩れない集合組織遺伝が発現する要因にもなっている。Ｍｏ，ＮｂおよびＢ量の下限は、それぞれ、０．１％、０．０１％、０．０００６％とする。これより少ない量の添加では、上述の３つの効果が十分得られず、最終的に得られる集合組織がランダムになってしまうからである。一方、Ｍｏ，Ｎｂ，Ｂをそれぞれ１．５％超、０．２％超、０．０１％超添加してもｒ値向上効果は飽和し、コストアップとなるので、これを上限とする。 In addition, since recrystallization during the subsequent annealing is also suppressed, it is effective to bring the texture after annealing without breaking the texture in hot rolling. In addition, these elements improve the hardenability during the γ → α transformation, so annealing in the two-phase region or single phase of the γ region, and the texture does not collapse even after going through the α → γ → α transformation It is also a factor in inheritance. The lower limits of the amounts of Mo, Nb, and B are 0.1%, 0.01%, and 0.0006%, respectively. This is because if the amount is less than this, the above three effects cannot be sufficiently obtained, and the finally obtained texture becomes random. On the other hand, even if Mo, Nb, and B are added in excess of 1.5%, 0.2%, and 0.01%, respectively, the effect of improving the r value is saturated and the cost is increased.
Ａｌは、脱酸調製剤として使用しても良い。ただし、Ａｌは変態点を著しく高めるので低温γ域での圧延が困難となるので、上限を０．１５％とする。下限は特に定めないが、脱酸の観点から、０．０１％以上とすることが好ましい。
Ｎは、Ｂと窒化物を形成し、Ｂの再結晶抑制効果を低減させることから０．０１％以下に抑える。この観点から望ましくは０．００５％、更に望ましくは０．００２％以下とする。Ｎの下限は特に設定しないが０．０００５％未満とすることにはコストがかかるばかりでそれほどの効果が得られないことから０．０００５％以上とすることが望ましい。
Al may be used as a deoxidation preparation agent. However, since Al significantly raises the transformation point, rolling in the low temperature γ region becomes difficult, so the upper limit is made 0.15%. The lower limit is not particularly defined, but is preferably 0.01% or more from the viewpoint of deoxidation.
N forms nitrides with B and reduces the recrystallization suppressing effect of B, so it is suppressed to 0.01% or less. From this viewpoint, it is preferably 0.005%, and more preferably 0.002% or less. The lower limit of N is not particularly set, but if it is less than 0.0005%, it is not only costly, but not so much effect is obtained, so 0.0005% or more is desirable.
Ｔｉは、γ高温域でＮと窒化物を形成し、ＢＮの生成を抑制する。また、熱延中の再結晶抑制効果も期待できることから４８／１４×Ｎ（ｍａｓｓ％）以上添加する。ただし、０．２％超添加しても特段の効果が得られないばかりか、加工性が劣化することからこの値を上限とする。好ましくは、０．０９％以下である。
Ｃａは、脱酸元素として有用であるほか、硫化物の形態制御にも効果を奏するので、０．０００５〜０．０１％の範囲で添加しても良い。０．０００５％未満では効果が十分でなく、０．０１％超添加すると加工性が劣化するのでこの範囲とする。
Ti forms nitrides with N in the γ high temperature region and suppresses the generation of BN. Further, since the effect of suppressing recrystallization during hot rolling can be expected, 48/14 × N (mass%) or more is added. However, even if adding over 0.2%, not only a special effect is not obtained, but also workability deteriorates, so this value is made the upper limit. Preferably, it is 0.09% or less.
Ca is useful as a deoxidizing element and also has an effect on controlling the form of sulfide, so Ca may be added in the range of 0.0005 to 0.01%. If it is less than 0.0005%, the effect is not sufficient, and if it exceeds 0.01%, the workability deteriorates, so this range is set.
これらを主成分とする鋼に、機械的強度を高めたり材質を改善する目的で、Ｓｎ，Ｃｏ，Ｚｎ，Ｗ，Ｚｒ，Ｍｇ，Ｒｅｍの１種又は２種以上を合計で０．００１〜１％以下含有しても構わない。しかしながら、ＺｒはＺｒＮを形成するため固溶Ｎが減少するので０．０１％以下とすることが好ましい。
Ｎｉ，Ｃｕ，Ｃｒは低温γ域圧延を行うためには有利な元素であるので、これらの１種又は２種以上を合計で０．００１〜４．０％の範囲で添加しても良い。０．００１％未満では顕著な効果が得られず、４．０％超添加すると加工性が劣化する。
In order to increase the mechanical strength or improve the material of these steels as the main component, one or more of Sn, Co, Zn, W, Zr, Mg, and Rem are added in a total amount of 0.001-1. % Or less may be contained. However, since Zr forms ZrN and solid solution N decreases, it is preferably made 0.01% or less.
Since Ni, Cu, and Cr are elements that are advantageous for performing low-temperature γ region rolling, one or more of these may be added in a range of 0.001 to 4.0% in total. If it is less than 0.001%, a remarkable effect cannot be obtained, and if it exceeds 4.0%, workability deteriorates.
次に集合組織について説明する。
板厚１／２層における｛３３２｝＜１１３＞方位の極密度は４．５以上とする。これによってｒ値、特に圧延方向および幅方向のｒ値を高めることが可能となる。この観点から極密度は６以上とすることが望ましく、更に望ましくは８以上とする。一方、板厚１／２層における｛１００｝＜０１１＞方位の極密度は３以下とする。この方位はｒ値を下げる方位のため、出来る限り低減することが望ましい。この観点から好ましくは１．５以下とする。
Next, the texture will be described.
The pole density in the {332} <113> orientation in the ½ layer thickness is 4.5 or more. This makes it possible to increase the r value, particularly the r value in the rolling direction and the width direction. From this viewpoint, the pole density is desirably 6 or more, and more desirably 8 or more. On the other hand, the pole density in the {100} <011> orientation in the 1/2 layer thickness is 3 or less. Since this orientation is an orientation that lowers the r value, it is desirable to reduce it as much as possible. From this viewpoint, it is preferably 1.5 or less.
板厚１／８層における｛１１０｝＜２２３＞及び／又は｛１１０｝＜１１１＞の極密度は４以下とすることが望ましい。この結晶方位は熱延板の表層にできる剪断集合組織の主方位で圧延方向および幅方向のｒ値を下げる。したがって、この観点から望ましくは上記の極密度の上限は３以下とする。これらの方位の極密度（Ｘ線ランダム強度比）は、Ｘ線回折によって測定される｛１１０｝，｛１００｝，｛２１１｝，｛３１０｝極点図のうち複数の極点図を基に級数展開法で計算した３次元集合組織（ＯＤＦ）から求めればよい。すなわち、各結晶方位の極密度を求めるには、３次元集合組織のφ２＝４５°断面における（３３２）［−１−１３］、（００１）［１−１０］の強度で代表させる。上記の１／２板厚での極密度に関する限定は少なくとも板厚１／２層については満足し、実際には１／２層のみならず、板厚表層までの広い範囲で成り立つことが好ましいことは言うまでもない。 The pole density of {110} <223> and / or {110} <111> in the plate thickness 1/8 layer is preferably 4 or less. This crystal orientation is the main orientation of the shear texture formed on the surface layer of the hot-rolled sheet, and lowers the r value in the rolling direction and the width direction. Therefore, the upper limit of the above-mentioned pole density is desirably 3 or less from this viewpoint. The pole density (X-ray random intensity ratio) of these orientations is developed in series based on a plurality of pole figures among {110}, {100}, {211}, {310} pole figures measured by X-ray diffraction. What is necessary is just to obtain | require from the three-dimensional texture (ODF) calculated by the method. That is, in order to obtain the pole density of each crystal orientation, it is represented by the intensity of (332) [-1-13] and (001) [1-10] in the φ2 = 45 ° cross section of the three-dimensional texture. The above-mentioned limitation regarding the pole density at 1/2 plate thickness is satisfied for at least 1/2 layer thickness, and in fact, it is preferable to hold not only 1/2 layer but also a wide range up to the plate thickness surface layer. Needless to say.
Ｘ線回折用試料の作製は次のようにして行う。
鋼板を機械研磨や化学研磨などによって板厚方向に所定の位置まで研磨し、バフ研磨によって鏡面に仕上げた後、電解研磨や化学研磨によって歪みを除去すると同時に板厚１／８層または１／２層が測定面となるように調整する。なお、正確に板厚１／８層や１／２層を測定面とすることは困難であるので、これら目標とする層を中心として板厚に対して±３％の範囲が測定面となるように試料を作製すればよい。また、鋼板の板厚中心層に偏析帯が認められる場合には、板厚の３／８〜５／８の範囲で偏析帯のない場所について測定すればよい。さらにＸ線測定が困難な場合には、ＥＢＳＰ法やＥＣＰ法により統計的に十分な数の測定を行う。
The sample for X-ray diffraction is manufactured as follows.
The steel plate is polished to a predetermined position in the plate thickness direction by mechanical polishing or chemical polishing, and finished to a mirror surface by buffing, and then the strain is removed by electrolytic polishing or chemical polishing, and at the same time the plate thickness is 1/8 layer or 1/2 Adjust the layer to be the measurement surface. In addition, since it is difficult to accurately set the plate thickness 1/8 layer or 1/2 layer as the measurement surface, the measurement surface has a range of ± 3% with respect to the plate thickness centering on these target layers. A sample may be prepared as described above. Moreover, when a segregation band is recognized in the plate thickness center layer of the steel sheet, it may be measured in a place where there is no segregation band in the range of 3/8 to 5/8 of the plate thickness. Further, when X-ray measurement is difficult, a statistically sufficient number of measurements are performed by the EBSP method or the ECP method.
なお、｛ｈｋｌ｝＜ｕｖｗ＞とは上述の方法でＸ線用試料を採取したとき、板面に垂直な結晶方位が＜ｈｋｌ＞で圧延方向に平行な方位が＜ｕｖｗ＞であることを意味する。
最終的に得られた鋼板のｒ値の下限値は１．０とする。ｒ値が１．０未満の方向があると平均ｒ値が高くても良好な成形性が確保できない。この観点から望ましくは１．１以上とする。また、平均ｒ値の下限値は１．３とする。平均ｒ値が１．３未満では良好な成形性を発揮することが出来ない。この観点から平均ｒ値は１．４以上とすることが望ましい。
Note that {hkl} <uvw> means that when an X-ray sample is collected by the above method, the crystal orientation perpendicular to the plate surface is <hkl> and the orientation parallel to the rolling direction is <uvw>. To do.
The lower limit of the r value of the finally obtained steel sheet is 1.0. If the r value is less than 1.0, good moldability cannot be ensured even if the average r value is high. From this viewpoint, it is desirably 1.1 or more. The lower limit value of the average r value is 1.3. If the average r value is less than 1.3, good moldability cannot be exhibited. From this viewpoint, the average r value is desirably 1.4 or more.
ｒ値はＪＩＳ５号引張試験片を用いた引張試験により評価する。引張歪みは通常１５％であるが、均一伸びが１５％を下回る場合には、均一伸びの範囲でできるだけ１５％に近い歪みで評価すればよい。
ｒ値の下限値は圧延方向、圧延４５°方向、幅方向から切り出した試験片で測定した値のうち最低の値で代表してもよいし、更に任意の方向から切り出した試験片での測定結果を加えて評価してもよい。また、集合組織の測定結果からの計算値で求めてもよい。
ｒ値の平均値は圧延方向のｒ値（ｒＬ）、４５°方向のｒ値（ｒＸ）、幅方向のｒ値（ｒＣ）より次のように求める。
平均ｒ値＝（ｒＬ＋２×ｒＸ＋ｒＣ）／４
The r value is evaluated by a tensile test using a JIS No. 5 tensile test piece. The tensile strain is usually 15%, but when the uniform elongation is less than 15%, the strain may be evaluated as close to 15% as possible within the range of uniform elongation.
The lower limit of the r value may be represented by the lowest value among the values measured with the test piece cut from the rolling direction, the 45 ° direction, and the width direction, and further measured with a test piece cut from any direction. You may evaluate by adding a result. Moreover, you may obtain | require by the calculated value from the measurement result of a texture.
The average value of the r values is determined as follows from the r value (rL) in the rolling direction, the r value (rX) in the 45 ° direction, and the r value (rC) in the width direction.
Average r value = (rL + 2 × rX + rC) / 4
次に、製造条件の限定理由について述べる。
熱間圧延に供するスラブは本発明に規定する成分からなるものであれば、特に限定するものではない。すなわち、連続鋳造スラブや薄スラブキャスターなどで製造したものであればよい。また、鋳造後に直ちに熱間圧延を行う連続鋳造−直接圧延（ＣＣ−ＤＲ）のようなプロセスにも適合する。
熱延加熱温度は１１００℃以上とする。これは、炭化物を際溶解するのに必要な温度である。この観点から望ましくは１１５０℃、更に望ましくは１２００℃以上で加熱をする。熱間圧延を行う際には（１）式で計算される有効ひずみ量ε* が０．４以上かつ圧下率の合計が５０％以上となるようにする。
Next, the reasons for limiting the manufacturing conditions will be described.
The slab to be subjected to hot rolling is not particularly limited as long as it is composed of the components specified in the present invention. That is, what was manufactured with the continuous casting slab, the thin slab caster, etc. should just be used. It is also compatible with processes such as continuous casting-direct rolling (CC-DR) in which hot rolling is performed immediately after casting.
The hot rolling heating temperature is 1100 ° C. or higher. This is the temperature necessary to dissolve the carbide. From this viewpoint, the heating is preferably performed at 1150 ° C., more preferably 1200 ° C. or more. When performing hot rolling, the effective strain amount ε * calculated by the equation (1) is 0.4 or more and the total rolling reduction is 50% or more.
ここで、ｎは仕上げ熱延の圧延スタンド数、εｉはｉ番目のスタンドで加えられたひずみ、ｔｉはｉ〜ｉ＋１番目のスタンド間の走行時間（秒）、τｉは気体常数Ｒ（＝１．９８７）とｉ番目のスタンドの圧延温度Ｔｉ（Ｋ）によって下式で計算できる。
τｉ＝８．４６×１０-9・ｅｘｐ｛４３８００／Ｒ／Ｔｉ｝
有効ひずみε* は０．５以上が好ましく、０．６以上であればより好ましい。圧下率の合計は７０％以上がより好ましい。圧下率の合計とは、ｎパスの圧延の場合、１パス目〜ｎパス目までの各圧下率をＲ1 （％）〜Ｒｎ（％）とすると、Ｒ1 ＋Ｒ2 ＋‥‥＋Ｒｎと定義する。Ｒｎ＝｛（ｎ−１）パス後の板厚−ｎパス後の板厚｝／（ｎ−１）パス後の板厚×１００（％）である。
Here, n is the number of rolling stands for finish hot rolling, εi is the strain applied at the i-th stand, ti is the travel time (seconds) between i to i + 1th stands, and τi is the gas constant R (= 1. 987) and the rolling temperature Ti (K) of the i-th stand can be calculated by the following equation.
τi = 8.46 × 10 −9 · exp {43800 / R / Ti}
The effective strain ε * is preferably 0.5 or more, more preferably 0.6 or more. The total rolling reduction is more preferably 70% or more. The total reduction ratio is defined as R 1 + R 2 +... + Rn, where each reduction ratio from the 1st pass to the nth pass is R 1 (%) to Rn (%) in the case of n-pass rolling. To do. Rn = {plate thickness after (n−1) pass−plate thickness after n pass} / (n−1) plate thickness after pass × 100 (%).
熱延の仕上温度は、Ａｒ3 変態点以上とする。Ａｒ3 変態点未満では、表層、板厚中心共にｒ値にとって好ましくない集合組織が発達してしまう。また仕上温度は９００℃以下とする。９００℃超では、熱延中に加工ひずみが蓄積出来ず、ｒ値に好ましい集合組織を発達させることが困難である。この観点から好ましくは８５０℃以下、更に好ましくは８００℃以下とする。 The finishing temperature of hot rolling is not less than the Ar 3 transformation point. Below the Ar 3 transformation point, a texture unfavorable for the r value develops at both the surface layer and the thickness center. The finishing temperature is 900 ° C. or lower. If it exceeds 900 ° C., processing strain cannot be accumulated during hot rolling, and it is difficult to develop a texture suitable for the r value. From this viewpoint, the temperature is preferably 850 ° C. or lower, more preferably 800 ° C. or lower.
熱延後の巻き取り温度が７００℃超になると熱延中に形成された集合組織が弱くなりｒ値が低下することからこの温度を上限とする。下限は特に限定しないが４００℃未満で巻き取ると熱延板の強度が高くなりすぎ、冷延の負荷が高くなることから４００℃以上で巻き取ることが好ましい。
本発明の温度範囲での熱間圧延は通常の条件で行われても最終的な鋼板のｒ値は向上するが、この温度範囲で行われる熱間圧延の少なくとも１パス以上においてその摩擦係数が０．２以下となるように制御した場合には更にｒ値が向上する。この観点からは２パス以上の圧延で摩擦係数が０．２以下になることが望ましい。
When the coiling temperature after hot rolling exceeds 700 ° C., the texture formed during hot rolling becomes weak and the r value decreases, so this temperature is made the upper limit. Although the lower limit is not particularly limited, it is preferable to wind at 400 ° C. or higher because the strength of the hot rolled sheet becomes too high when it is wound at less than 400 ° C., and the cold rolling load increases.
The hot rolling in the temperature range of the present invention improves the r value of the final steel sheet even if it is performed under normal conditions, but the friction coefficient is at least one pass or more of the hot rolling performed in this temperature range. When it is controlled to be 0.2 or less, the r value is further improved. From this point of view, it is desirable that the friction coefficient be 0.2 or less in rolling of 2 passes or more.
熱延鋼板は酸洗後、冷間圧延を行う。冷間圧延率の下限は３０％超とする。圧延率を３０％以下にすると、熱延板の表層に形成されている剪断集合組織が冷延・焼鈍後まで残存し、ｒ値を低下させることからこの値を下限とする。一方、圧延率が７０％超となると、ｒ値を低下させる｛１００｝＜０１１＞方位が発達し、最終的に得られるｒ値が低下する。この観点から圧延率の上限は好ましくは６０％以下、更に、望ましくは５０％以下とする。 The hot-rolled steel sheet is cold-rolled after pickling. The lower limit of the cold rolling rate is over 30%. If the rolling rate is 30% or less, the shear texture formed on the surface layer of the hot-rolled sheet remains until after cold rolling and annealing, and the r value is lowered, so this value is set as the lower limit. On the other hand, when the rolling ratio exceeds 70%, the {100} <011> orientation that lowers the r value develops and the finally obtained r value decreases. From this viewpoint, the upper limit of the rolling rate is preferably 60% or less, and more preferably 50% or less.
冷延後の連続焼鈍の加熱速度の下限は３℃／ｓとする。加熱速度が３℃／ｓ未満となると加熱中に再結晶が進行し、集合組織が劣化する。この観点から望ましくは５℃／ｓ以上する。１０℃／ｓ以上とすることが更に望ましい。一方、加熱速度の上限は５０℃／ｓとする。加熱速度を５０℃／ｓ超としても特段の効果が得られないばかりでなく、設備への負荷が高くなりすぎるためこの値を上限とする。 The lower limit of the heating rate of continuous annealing after cold rolling is 3 ° C./s. When the heating rate is less than 3 ° C./s, recrystallization proceeds during heating and the texture deteriorates. From this viewpoint, it is preferably 5 ° C./s or more. It is more desirable to set it as 10 degree-C / s or more. On the other hand, the upper limit of the heating rate is 50 ° C./s. Even if the heating rate exceeds 50 ° C./s, not only a special effect cannot be obtained, but the load on the equipment becomes too high, so this value is made the upper limit.
最高到達温度は５００〜９５０℃の範囲とする。最高到達温度が５００℃未満では加工フェライトが残存し、成形性が劣化するため、これを下限とする。この観点から望ましくは６００℃以上とする。また、変態組織強化を利用する場合にはＡｃ1 点を最高到達温度の下限とする。一方で、熱処理温度を９５０℃超とするとγ相中での粒成長が進行し、集合組織がランダムかするため、この温度を上限とする。この観点から望ましくはＡｃ3 ＋５０℃以下とすることが望ましい。 The maximum temperature reached is in the range of 500 to 950 ° C. If the maximum temperature reached is less than 500 ° C., the processed ferrite remains and the formability deteriorates, so this is the lower limit. From this viewpoint, the temperature is desirably 600 ° C. or higher. Further, when utilizing transformation structure strengthening, Ac 1 point is set as the lower limit of the maximum temperature reached. On the other hand, if the heat treatment temperature exceeds 950 ° C., grain growth proceeds in the γ phase and the texture becomes random, so this temperature is set as the upper limit. From this point of view, it is desirable to set Ac 3 + 50 ° C. or lower.
同熱処理後に一旦５５０℃以下まで冷却し、さらに１５０〜５５０℃の温度で熱処理を施すことも可能である。これは、固溶Ｃ量の制御やマルテンサイトの焼き戻し、ベイナイト変態の促進等の組織制御など、種々の目的に応じて適当な条件を選択して行えば良い。熱処理後には溶融亜鉛めっき、または合金化溶融亜鉛めっきを施してもよい。亜鉛めっきの組成は特に限定するものではなく、亜鉛のほか、Ｆｅ、Ａｌ、Ｍｎ、Ｃｒ、Ｍｇ、Ｐｂ、Ｓｎ、Ｎｉなどを必要に応じて添加しても構わない。合金化処理は４５０〜６００℃の範囲内で行う。４５０℃未満では合金化が十分に進行せず、また、６００℃超では過度に合金化が進行し、めっき層が脆化するため、プレス等の加工によってめっきが剥離するなどの問題を誘発する。合金化処理の時間は、１０ｓ以上とする。１０ｓ未満では合金化が十分に進行しない。 After the heat treatment, it can be once cooled to 550 ° C. or lower and further subjected to heat treatment at a temperature of 150 to 550 ° C. This may be done by selecting appropriate conditions according to various purposes such as control of the amount of dissolved C, tempering of martensite, and structure control such as promotion of bainite transformation. After the heat treatment, hot dip galvanizing or alloying hot dip galvanizing may be performed. The composition of the galvanizing is not particularly limited, and besides zinc, Fe, Al, Mn, Cr, Mg, Pb, Sn, Ni, etc. may be added as necessary. The alloying treatment is performed within a range of 450 to 600 ° C. If it is less than 450 ° C, alloying does not proceed sufficiently, and if it exceeds 600 ° C, alloying proceeds excessively and the plating layer becomes brittle, which causes problems such as peeling of the plating by processing such as pressing. . The alloying treatment time is 10 s or longer. If it is less than 10 s, alloying does not proceed sufficiently.
本発明によって得られる鋼板の組織は、フェライトまたはベイナイトを主相とするが、両相が混在していても構わないし、これらにマルテンサイト、オーステナイト、炭化物、窒化物を初めとする化合物が存在していても良い。すなわち、要求特性に応じて組織を作り分ければ良い。また、上記の冷延鋼板にはＡｌ系めっきや各種電気めっきを施しても構わない。
次に本発明を実施例にて説明する。
The structure of the steel sheet obtained by the present invention has ferrite or bainite as a main phase, but both phases may be mixed, and these include compounds such as martensite, austenite, carbide, and nitride. May be. That is, it is only necessary to create an organization according to required characteristics. Moreover, you may give Al type plating and various electroplating to said cold-rolled steel plate.
Next, the present invention will be described with reference to examples.
表１に示す組成を有する鋼を溶製し、表２に示す条件で熱間圧延、冷間圧延、焼鈍を施した。このとき熱延の加熱温度は全て１２３０℃とした。また、焼鈍熱延調質圧延圧下率はすべて０．５％とした。ｒ値はＪＩＳ５号引張試験片を採取して評価した。また、板厚１／８層および板厚７／１６層における集合組織をＸ線で測定した。表３より明らかなとおり、本発明の化学成分を有する鋼を適正な条件で製造した場合には、ｒ値の下限値が１．０以上、平均ｒ値が１．３以上の深絞り性に優れた鋼板が得られることがわかる。 Steel having the composition shown in Table 1 was melted and subjected to hot rolling, cold rolling, and annealing under the conditions shown in Table 2. At this time, the heating temperature of hot rolling was all set to 1230 ° C. Moreover, all the annealing hot rolling temper rolling reduction ratios were 0.5%. The r value was evaluated by collecting a JIS No. 5 tensile test piece. Further, the texture in the plate thickness 1/8 layer and the plate thickness 7/16 layer was measured by X-ray. As is apparent from Table 3, when the steel having the chemical composition of the present invention is produced under appropriate conditions, the lower limit value of the r value is 1.0 or more, and the average r value is 1.3 or more. It can be seen that an excellent steel sheet can be obtained.
代理人 弁理士 椎 名 彊 他１
Attorney Attorney Shiina and others 1
Claims (9)
Ｃ：０．０１〜０．３％、
Ｓｉ：２．５％以下、
Ｍｎ：０．１〜３．０％、
Ｐ：０．１５％以下、
Ｓ：０．０１５％以下、
Ｍｏ：０．１〜１．５％、
Ｂ：０．０００６〜０．０１％、
Ａｌ：０．１５％以下、
Ｎｂ：０．０１〜０．２０％、
Ｎ：０．０１％以下、
Ｔｉ：４８／１４×Ｎ（質量％）以上、０．２％以下
を含有し、残部鉄及び不可避的不純物からなり、板厚１／２層における｛３３２｝＜１１３＞の極密度が４．５以上でかつ｛１００｝＜０１１＞の極密度が３以下、更に圧延方向と４５度方向と幅方向のｒ値の最小値が１．０以上で、かつ圧延方向と４５度方向と幅方向の平均ｒ値が１．３以上であることを特徴とする深絞り性に優れた高強度冷延鋼板。 % By mass
C: 0.01 to 0.3%,
Si: 2.5% or less,
Mn: 0.1 to 3.0%
P: 0.15% or less,
S: 0.015% or less,
Mo: 0.1 to 1.5%,
B: 0.0006 to 0.01%
Al: 0.15% or less,
Nb: 0.01-0.20%,
N: 0.01% or less,
Ti: 48/14 × N (mass%) or more and 0.2% or less, consisting of the balance iron and unavoidable impurities, the pole density of {332} <113> in the 1/2 layer thickness is 4. 5 or more and {100} <011> pole density of 3 or less, and the minimum r value in the rolling direction, 45 degree direction and width direction is 1.0 or more, and the rolling direction, 45 degree direction and width direction. A high-strength cold-rolled steel sheet excellent in deep drawability, characterized by having an average r value of 1.3 or more.
τｉ＝８．４６×１０−９・ｅｘｐ｛４３８００／Ｒ／Ｔｉ｝ When the slab having the chemical component according to any one of claims 1 and 3 to 5 is heated to a temperature of 1100 ° C or higher and hot-rolled, the effective strain amount calculated by the formula (1) Rolling is performed so that ε * is 0.4 or more and the total reduction ratio is 50% or more. After hot rolling is completed at a temperature of Ar 3 transformation point to 900 ° C., winding is performed at 700 ° C. or less. In addition, after performing cold rolling with a rolling reduction of more than 30% and 70% or less, annealing is performed at a heating rate of 3 to 50 ° C./s so that the temperature reaches a maximum temperature of 500 ° C. or more and 950 ° C. or less. The manufacturing method of the high intensity | strength cold-rolled steel plate excellent in the deep drawability of any one of Claims 1-5.
τi = 8.46 × 10 −9 · exp {43800 / R / Ti}
The method for producing an alloyed hot-dip galvanized steel sheet according to claim 8, wherein after the hot-dip galvanizing, heat treatment is performed for 10 seconds or more in a temperature range from 450 to 600 ° C.
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