JPH10102191A - Stock for steel sheet for can, excellent in ridging resistance and deep drawability after cold rolling-annealing - Google Patents
Stock for steel sheet for can, excellent in ridging resistance and deep drawability after cold rolling-annealingInfo
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- JPH10102191A JPH10102191A JP25609296A JP25609296A JPH10102191A JP H10102191 A JPH10102191 A JP H10102191A JP 25609296 A JP25609296 A JP 25609296A JP 25609296 A JP25609296 A JP 25609296A JP H10102191 A JPH10102191 A JP H10102191A
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- Prior art keywords
- colony
- steel sheet
- rolling
- less
- annealing
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【0001】[0001]
【発明の属する技術分野】この発明は、省エネルギー
化、圧延ロールの長寿命化及び酸洗コスト低減を目的
に、低温仕上熱間圧延(フェライト域仕上圧延)を施し
ても、2ピースあるいは3ピース缶用鋼板等の使途に有
用な深絞り性に優れた鋼板を得ることができ、かつ、缶
体として加工を施した際にリジングが発生しない、缶用
鋼板用素材に関するものである。BACKGROUND OF THE INVENTION The present invention relates to a two-piece or three-piece hot rolling method for low-temperature finishing (ferrite finishing rolling) in order to save energy, extend the life of rolling rolls, and reduce pickling costs. The present invention relates to a material for a steel sheet for cans, which can provide a steel sheet having excellent deep drawability useful for uses such as a steel sheet for cans and does not generate ridging when processed as a can body.
【0002】[0002]
【従来の技術】種々の缶のなかでも特に2ピース缶に使
用される冷延鋼板には、その特性として優れた深絞り性
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r値(ランクフォード値)が必要であ
る。そのような深絞り用冷延鋼板には、Ar3 変態点以上
で熱間圧延を施したのち、冷間圧延により最終板厚の薄
板とし、しかる後に再結晶焼鈍を施して製造する冷延鋼
板が一般的に使用されていた。2. Description of the Related Art Among various types of cans, a cold-rolled steel sheet used for two-piece cans is required to have an excellent deep drawability as a characteristic. In order to improve the deep drawability, a high r value (Rankford value) is required as a mechanical property of the steel sheet. Such deep-drawn cold-rolled steel sheets are subjected to hot rolling at the Ar 3 transformation point or higher, then cold-rolled to a thin sheet of final thickness, and then subjected to recrystallization annealing to produce cold-rolled steel sheets Was commonly used.
【0003】近年、かかる冷延鋼板においては、熱延工
程の省エネルギー、歩留まり向上による低コスト化を目
的として、Ar3 変態点以下で仕上圧延を終了することが
試みられるようになった。しかし、実際にAr3 変態点以
下で仕上圧延を終了すると、「リジング」と呼ばれる特
異な現象を生じ易くなるところに問題があった。In recent years, in such cold-rolled steel sheets, attempts have been made to terminate finish rolling at a temperature not higher than the Ar 3 transformation point for the purpose of energy saving in the hot rolling process and cost reduction by improving yield. However, there is a problem in that when the finish rolling is actually finished below the Ar 3 transformation point, a peculiar phenomenon called “ridging” tends to occur.
【0004】このリジングとは、薄板に引張りや深絞り
等の変形を加えたとき、圧延方向に沿って細かい筋状の
しわを生ずる現象であり、一般に17%Crステンレス鋼の
ようなフェライト系ステンレス鋼では、「日本金属学会
会誌Vol.31,No.4(1967),p.519 」や「日本金属学会会誌
Vol.31,No.6(1967),p.717 」に開示されているようによ
く知られている現象である。[0004] This ridging is a phenomenon in which fine streak-like wrinkles are formed along the rolling direction when a thin plate is subjected to deformation such as tension or deep drawing. Generally, ferritic stainless steel such as 17% Cr stainless steel is used. For steel, see the Journal of the Japan Institute of Metals, Vol. 31, No. 4 (1967), p.
Vol. 31, No. 6 (1967), p. 717 ”.
【0005】従来、このリジングの発生はステンレス鋼
特有のものと思われていたが、一般の冷延鋼板でもAr3
変態点以下で仕上圧延を終了する場合に発生し易いこと
が知られるようになった。これらの缶用鋼板、ステンレ
ス鋼板や自動車用鋼板等は、機械的性質の他に表面の平
滑さ、美麗さもまた重要な特性であり、このようなリジ
ングが生じた場合には製品として致命的な欠陥になって
しまうことがある。Conventionally, the occurrence of the ridging had been believed stainless steel unique, Ar 3 in the general cold-rolled steel sheet
It has become known that this is likely to occur when finish rolling is completed at or below the transformation point. These steel plates for cans, stainless steel plates, and steel plates for automobiles are not only mechanical properties but also surface smoothness and beauty are also important properties, and when such ridging occurs, it is a fatal product. It can be a defect.
【0006】このような観点から、リジングの発生原因
及び発生機構について、鋼組成や製造方法等の種々の見
地から研究が進められているが、未だ統一された見解は
出されていない。また、リジングの抑制手段としては、
「鉄と鋼Vol.77,No.8(1991)p.84 」や「鉄と鋼Vol.78,N
o.4(1992)p.124」に開示されるような対策、すなわち、
粗圧延パス間時間を長くするとか、熱延板焼鈍あるいは
パス間焼鈍をするといった手段が提案されてきたが、こ
れらの方法は、低コストで薄鋼板を製造することを前提
としている深絞り用冷延鋼板の製造に適用しようとする
場合においては、適正かつ効率的な手段を提供するもの
ではなかった。From this point of view, research into the causes and mechanisms of ridging from various viewpoints, such as steel composition and manufacturing methods, has been made, but no unified opinion has yet been issued. In addition, as means for suppressing ridging,
`` Iron and Steel Vol. 77, No. 8 (1991) p. 84 '' and `` Iron and Steel Vol. 78, N
o.4 (1992) p.124 ''.
Means such as increasing the time between coarse rolling passes or performing hot-rolled sheet annealing or inter-pass annealing have been proposed.However, these methods are used for deep drawing, which is based on the premise of producing thin steel sheets at low cost. In the case where it is applied to the production of a cold-rolled steel sheet, it does not provide a proper and efficient means.
【0007】更に、特開昭63−121623号公報に
は、耐リジング性と化成処理性に優れる冷延鋼板の製造
方法に関し、C、N、S量とTi量とが特定の関係になる
鋼を熱間圧延する際、仕上温度を600 〜800 ℃とし、か
つ少なくとも1パスを潤滑油を用いて仕上げ、引き続き
圧下率50〜95%で冷間圧延し、次に再結晶焼鈍する方法
が開示されている。しかしながら、この方法では少なく
とも1パスを潤滑油を用いながら圧延する必要があるた
め、圧延時にスリップ等の問題が生じ、生産性が著しく
低下するおそれがあった。Further, Japanese Patent Application Laid-Open No. 63-121623 relates to a method for producing a cold-rolled steel sheet having excellent ridging resistance and chemical conversion treatment properties, and relates to a steel having a specific relationship between the amounts of C, N, S and Ti. Discloses a method in which a hot rolling is performed at a finishing temperature of 600 to 800 ° C. and at least one pass is finished with a lubricating oil, then cold rolled at a reduction of 50 to 95%, and then recrystallized and annealed. Have been. However, in this method, at least one pass needs to be rolled while using a lubricating oil, so that a problem such as slip occurs at the time of rolling, and there is a possibility that productivity may be significantly reduced.
【0008】[0008]
【発明が解決しようとする課題】この発明は、上記の問
題を有利に解決するもので、深絞り用冷延鋼板の素材と
なる熱延鋼板のコロニーに着目し、そのコロニーの状態
を規制することにより、熱間圧延工程の生産性の低下な
く製造することのできる、耐リジング性及び深絞り性に
優れる缶用鋼板用の素材を提案することを目的とする。The present invention advantageously solves the above-mentioned problems, and focuses on a colony of a hot-rolled steel sheet as a material of a cold-rolled steel sheet for deep drawing, and regulates the state of the colony. Accordingly, an object of the present invention is to propose a material for a steel plate for cans having excellent ridging resistance and deep drawability, which can be manufactured without reducing the productivity of the hot rolling step.
【0009】[0009]
【課題を解決するための手段】発明者らは、冷延鋼板の
耐リジング性及び深絞り性を改善すべく鋭意研究を重ね
た結果、以下のように、その素材である熱延鋼板を限定
することにより、耐リジング性に優れた深絞り用冷延鋼
板が製造可能となることを見出した。上記の知見に立脚
するこの発明の要旨構成は、次のとおりである。 C:0.0005〜0.0150wt%、Si:0.10wt%以下、Mn:
0.1 〜0.6 wt%、P:0.02wt%以下、S:0.02wt%以
下、Al:0.015 〜0.15wt%及びN:0.02wt%以下を基本
成分として含み、残部はFe及び不可避的不純物の組成よ
りなり、かつ平均結晶粒径dが35μm 以下、平均コロニ
ーサイズが80μm 以下及び下記に示すコロニー内の方位
集中度Sが0.8 以下であることを特徴とする冷延−焼鈍
後の耐リジング性及び深絞り性に優れる缶用鋼板用素
材。 記 S=X20゜/X30゜ ここに、 X30゜:隣接する結晶粒間の方位差が30°以内のコロニ
ー面積 X20゜:X30゜のうち、隣接する結晶粒間の方位差が20
°以内のコロニー面積 及び、 基本成分に加えて、Ti:0.001 〜0.020 wt%及びN
b:0.001 〜0.020 wt%の少なくとも1種を含有するこ
とを特徴とする冷延−焼鈍後の耐リジング性及び深絞り
性に優れる缶用鋼板用素材、及び、 基本成分に加えて、B:0.0001〜0.0030wt%を含有
することを特徴とする冷延−焼鈍後の耐リジング性及び
深絞り性に優れる缶用鋼板用素材。Means for Solving the Problems The inventors of the present invention have conducted intensive studies to improve the ridging resistance and deep drawability of a cold-rolled steel sheet, and as a result, have limited the hot-rolled steel sheet as follows. By doing so, it has been found that a cold-rolled steel sheet for deep drawing excellent in ridging resistance can be manufactured. The gist configuration of the present invention based on the above findings is as follows. C: 0.0005 to 0.0150 wt%, Si: 0.10 wt% or less, Mn:
0.1 to 0.6 wt%, P: 0.02 wt% or less, S: 0.02 wt% or less, Al: 0.015 to 0.15 wt% and N: 0.02 wt% or less as a basic component, and the balance is based on the composition of Fe and inevitable impurities. And the average crystal grain size d is 35 μm or less, the average colony size is 80 μm or less, and the orientation concentration S in the colony shown below is 0.8 or less. Cold rolling-ridging resistance and depth after annealing Material for steel plate for cans with excellent drawability. Here serial S = X 20 ° / X 30 °, X 30 °: adjacent colony area X 20 ° misorientation is within 30 ° between the crystal grains: among X 30 °, the orientation difference between adjacent grains Is 20
° In addition to the colony area and basic components, Ti: 0.001 to 0.020 wt% and N
b: A material for a steel sheet for cans having excellent ridging resistance and deep drawability after cold rolling and annealing, characterized by containing at least one of 0.001 to 0.020 wt%, and B: A material for steel sheets for cans having excellent ridging resistance and deep drawability after cold rolling and annealing, characterized by containing 0.0001 to 0.0030 wt%.
【0010】[0010]
【発明の実施の形態】以下、この発明の基礎となった研
究結果を述べる。C:0.002 wt%、Si:0.01wt%、Mn:
0.2 wt%、P:0.01wt%、S:0.005 wt%、Al:0.04wt
%、N:0.002 wt%及びNb:0.005 wt%を含有し、残部
はFe及び不可避的不純物の組成よりなるシートバーを12
00℃に加熱−均熱後、1050℃で1パス圧延後、700 〜Ar
3 変態点の温度域で50〜90%の圧下率にて2パス圧延し
た後、700 ℃,1時間のコイル巻取処理を施した。引き
続き90%の冷間圧延を施した後、750 ℃−20s の再結晶
焼鈍を施した。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS The results of research on which the present invention is based will be described below. C: 0.002 wt%, Si: 0.01 wt%, Mn:
0.2 wt%, P: 0.01 wt%, S: 0.005 wt%, Al: 0.04 wt
%, N: 0.002 wt% and Nb: 0.005 wt%, the balance being 12% of a sheet bar composed of Fe and unavoidable impurities.
After heating to 00 ° C-soaking, 1 pass rolling at 1050 ° C, 700 ~ Ar
After two-pass rolling in a temperature range of three transformation points at a rolling reduction of 50 to 90%, a coil winding treatment was performed at 700 ° C. for one hour. Subsequently, after cold rolling of 90%, recrystallization annealing at 750 ° C. for 20 seconds was performed.
【0011】図1に、冷延鋼板の耐リジング性に及ぼす
熱延鋼板のコロニー内の方位集中度及びコロニーサイズ
の影響を示す。なお、リジング評価指数は、JIS 5号引
張試験片に加工した冷延鋼板に15%引張歪を与えたもの
を目視により評価して求めた。リジング評価指数が2以
下のものは実用上問題のないリジングレベルである。ま
た、コロニー内の方位集中度は、Electron Back Scatte
ring Diffraction Patern にて板厚断面の鋼板の結晶方
位を各結晶ごとに測定し、隣接する結晶粒間の方位差が
20°以内及び30°以内の結晶粒群をそれぞれコロニーと
みなし、その面積の比にて求めた。すなわち、コロニー
内の方位集中度Sは、S=X20゜/X30゜、但しX
30゜:隣接する結晶粒間の方位差が30°以内のコロニー
面積、X20゜:X30゜のうち、隣接する結晶粒間の方位
差が20°以内のコロニー面積、とした。この図1からわ
かるように、冷延鋼板の耐リジング性は、フェライト域
熱延鋼板のコロニー内の方位集中度に強く依存し、コロ
ニー内の方位集中度Sが0.8 以下で、かつコロニーサイ
ズが80μm 以下の場合に耐リジング性に優れた缶用冷延
鋼板が製造可能となる。FIG. 1 shows the influence of the orientation concentration and the colony size in the colony of the hot-rolled steel sheet on the ridging resistance of the cold-rolled steel sheet. In addition, the ridging evaluation index was obtained by visually evaluating a cold-rolled steel sheet processed into a JIS No. 5 tensile test piece and having a 15% tensile strain. Those having a ridging evaluation index of 2 or less are ridging levels having no practical problem. Also, the degree of azimuth concentration in the colony is Electron Back Scatte
The crystal orientation of a steel sheet with a thick cross section is measured for each crystal using the ring Diffraction Patern, and the orientation difference between adjacent crystal grains is determined.
The crystal grain groups within 20 ° and within 30 ° were regarded as colonies, respectively, and were determined by their area ratio. That is, the azimuth concentration S in the colony is S = X 20 ° / X 30 °, where X
30 °: a colony area where the difference in orientation between adjacent crystal grains is within 30 °, and X 20 °: a colony area where the difference in orientation between adjacent crystal grains is within 20 ° among X 30 °. As can be seen from FIG. 1, the ridging resistance of the cold-rolled steel sheet strongly depends on the degree of orientation concentration in the colony of the hot-rolled steel sheet in the ferrite region. When it is 80 μm or less, a cold rolled steel sheet for cans having excellent ridging resistance can be manufactured.
【0012】発明者らは、以上の実験結果を基に種々検
討した結果、以下のようにこの発明を定めたのである。 (1) 鋼成分 (a) C:0.0005〜0.0150wt% Cは少なければ少ないほど深絞り性が向上するので好ま
しいが、その含有量が0.015 wt%以下ではさほど悪影響
を及ぼさないので0.015 wt%以下と限定した。一方、C
量が0.0005wt%より少ないと、結晶粒が粗大化し、目的
の粒径の熱延鋼板が得られないし、冷延・焼鈍後の結晶
粒も粗大化し、絞り加工時に鋼板表面の肌荒れが生じる
危険性ガあるために、下限を0.0005wt%とした。 (b) Si:0.10wt%以下 Siは、鋼を強化する作用があり、所望の強度に応じて必
要量を添加させるが、その添加量が0.10wt%を超えると
鋼板が過度に硬質化し、かつ深絞り性が劣るので0.10wt
%以下と限定した。 (c) Mn:0.1 〜0.6 wt% Mnは、不純物であるSによる熱延中の赤熱脆性を防止す
るために必要な成分であり、そのために0.1 wt%以上が
必要であるが、一方で0.6 wt%を超えるとスラブ圧延中
に割れを生じたり、鋼板が過度に硬質化するために0.1
〜0.6 wt%の範囲に限定した。As a result of various studies based on the above experimental results, the inventors have determined the present invention as follows. (1) Steel component (a) C: 0.0005 to 0.0150 wt% It is preferable that C is as small as possible, because the deep drawability is improved. However, if the content is 0.015 wt% or less, it does not exert much adverse effect, so 0.015 wt% or less. And limited. On the other hand, C
If the amount is less than 0.0005 wt%, the crystal grains become coarse, a hot-rolled steel sheet having a desired grain size cannot be obtained, and the crystal grains after cold rolling and annealing also become coarse, which may cause a rough surface of the steel sheet surface during drawing. The lower limit was set to 0.0005 wt% because of the nature of the material. (b) Si: 0.10 wt% or less Si has the effect of strengthening steel, and the necessary amount is added depending on the desired strength. However, if the added amount exceeds 0.10 wt%, the steel sheet becomes excessively hard, 0.10wt due to poor deep drawability
% Or less. (c) Mn: 0.1 to 0.6 wt% Mn is a component necessary for preventing red hot embrittlement during hot rolling due to S as an impurity. Therefore, 0.1 wt% or more is required. If the content exceeds wt%, cracks may occur during slab rolling, or the steel sheet may become excessively hard.
Limited to the range of ~ 0.6 wt%.
【0013】(d) P:0.02wt%以下 Pは、鋼を強化する作用があり、所望の強度に応じて必
要量を添加させるが、その添加量が0.02wt%を超えると
深絞り性が劣るので、0.02wt%以下と限定した。 (e) S:0.02wt%以下 Sは、熱延中の赤熱脆性を生じさせく不純物成分であ
り、極力少ないことが望ましいが、不可避的に含有され
る成分でもあるため、上限を0.02wt%とした。(D) P: not more than 0.02 wt% P has the effect of strengthening the steel, and the necessary amount is added according to the desired strength. If the added amount exceeds 0.02 wt%, the deep drawability becomes poor. Since it is inferior, it was limited to 0.02 wt% or less. (e) S: 0.02 wt% or less S is an impurity component that causes red hot embrittlement during hot rolling, and is desirably as small as possible. However, since it is an unavoidable component, the upper limit is 0.02 wt%. And
【0014】(f) Al:0.015 〜0.15wt% Alは脱酸を行い、炭窒化物形成成分の歩留まり向上のた
めに必要に応じて添加されるが、の含有量が0.015 wt%
未満だと添加効果がなく、一方0.15wt%を超えて添加し
ても、より一層の脱酸効果は得られないため、0.015 〜
0.15wt%に限定した。 (g) N:0.02wt%以下 Nは、少なければ少ないほど深絞り性が向上するので好
ましいが、その含有量が0.02wt%以下ではさほど悪影響
を及ぼさないので、0.02wt%以下に限定した。(F) Al: 0.015 to 0.15 wt% Al is deoxidized and added as needed to improve the yield of carbonitride forming components, but the content of Al is 0.015 wt%.
If it is less than 0.15% by weight, no additional effect will be obtained.
Limited to 0.15 wt%. (g) N: 0.02 wt% or less N is preferably as small as possible because the deep drawability is improved. However, if the content of N is 0.02 wt% or less, there is no significant adverse effect, so N was limited to 0.02 wt% or less.
【0015】上記の基本成分に加えて、この発明では、
Ti、Nbの一種以上又は/及びBを含有させることが可能
である。 (h) Ti:0.001 〜0.02wt% Tiは、鋼中の固溶Cを炭化物として析出固定させて低減
し、固溶Cによる深絞り性劣化防止する効果がある。そ
の添加量が0.001 wt%以下では添加効果がなく、一方、
0.02wt%を超えて添加しても、それ以上の効果は得られ
ず、逆に深絞り性劣化につながるので、0.001 〜0.02wt
%に限定した。 (i)Nb :0.001 〜0.02wt% Nbは、鋼中の固溶Cを炭化物として析出固定させて低減
し、固溶Cによる深絞り性劣化を防止する効果がある。
その添加量が0.001 wt%未満では添加効果がなく、一方
0.02wt%を超えて添加してもそれ以上の効果は得られ
ず、逆に深絞り性劣化につながるので、0.001 〜0.02wt
%に限定した。 (j) B:0.0001〜0.0030wt% Bは、鋼の耐二次加工脆性の改善のために添加される
が、その添加量が0.0001wt%未満では添加効果がなく、
一方0.0030wt%を超えて添加すると、逆に深絞り性劣化
につながるので、0.0001〜0.0030wt%に限定した。In addition to the above basic components, the present invention provides
One or more of Ti and Nb and / or B can be contained. (h) Ti: 0.001 to 0.02 wt% Ti is reduced by precipitating and fixing solid solution C in steel as a carbide, and has an effect of preventing deep drawability deterioration due to solid solution C. When the amount is 0.001 wt% or less, there is no effect of addition, while
Even if added in excess of 0.02 wt%, no further effect can be obtained, and conversely, deep drawability is deteriorated.
%. (i) Nb: 0.001 to 0.02 wt% Nb has an effect of reducing solid solution C in steel by precipitation and fixing it as carbide, thereby preventing deep drawability deterioration due to solid solution C.
If the addition amount is less than 0.001 wt%, there is no addition effect, while
Even if added in excess of 0.02 wt%, no further effect is obtained, and conversely, deep drawability is deteriorated, so 0.001 to 0.02 wt%
%. (j) B: 0.0001 to 0.0030 wt% B is added for improving the resistance to secondary working brittleness of steel. However, if the addition amount is less than 0.0001 wt%, there is no addition effect.
On the other hand, if added in excess of 0.0030 wt%, on the contrary, deep drawability will deteriorate, so the content was limited to 0.0001 to 0.0030 wt%.
【0016】(2) 熱延鋼板のコロニー内の方位集中度 熱延鋼板のコロニー内の方位集中度は、この発明におい
て最も重要であり、冷延−焼鈍後の耐リジング性を改善
するためは、熱延鋼板のコロニー内の方位集中度を0.8
以下にする必要がある。すなわち、熱延板にてコロニー
内の方位集中度が0.8 より高い場合は、たとえ鋼成分及
び冷延−焼鈍条件を変化させても、優れた耐リジング性
は得られない。(2) The degree of orientation concentration in the colony of the hot-rolled steel sheet The degree of orientation concentration in the colony of the hot-rolled steel sheet is most important in the present invention. In order to improve the ridging resistance after cold rolling and annealing, 0.8 degree of orientation concentration in the colony of hot rolled steel
It must be: That is, when the degree of orientation concentration in the colony of the hot-rolled sheet is higher than 0.8, excellent ridging resistance cannot be obtained even if the steel composition and the cold-rolling-annealing conditions are changed.
【0017】なお、コロニー内の方位集中度の規制によ
る耐リジング性改善の効果に関しては、以下のように考
えられる。発明者らは、フェライト域熱延材の耐リジン
グ性に関して、種々の検討を行った結果、耐リジング性
に最も影響を与える因子として、熱延板で形成されてい
るコロニー(隣接する結晶粒間の方位差が数十度以内の
結晶粒群)であることを、Electron Back Scattering D
iffraction Patern を用いた研究により明らかにした。
そして、耐リジング性を改善するためには、コロニー内
の結晶粒をランダムにすることが最も有効であることを
見出した。そのコロニー内の結晶粒のランダム化の程度
をコロニー内の方位集中度:Sで表せることを種々の実
験により見出し、 S=X20゜/X30゜ ここに、 X30゜:隣接する結晶粒間の方位差が30°以内のコロニ
ー面積 X20゜:X30゜のうち、隣接する結晶粒間の方位差が20
°以内のコロニー面積 とした。The effect of improving ridging resistance by regulating the degree of azimuth concentration in a colony is considered as follows. The present inventors have conducted various studies on the ridging resistance of the hot-rolled material in the ferrite region. As a result, the most influential factor of the ridging resistance was the colony formed on the hot-rolled sheet (between adjacent crystal grains). (Electron Back Scattering D)
A study using iffraction patern revealed this.
And it has been found that randomizing the crystal grains in the colonies is most effective for improving the ridging resistance. Orientation degree of concentration in the colonies of the degree of randomization of the crystal grains in that colony: Heading by various experiments that expressed by S, here S = X 20 ° / X 30 °, X 30 °: adjacent crystal grains colonies area X 20 ° misorientation is within 30 ° between: among X 30 °, the orientation difference between adjacent grains is 20
The colony area was within °.
【0018】なお、フェライト域熱延板に形成されるコ
ロニーをランダム化するためには、コロニー内の結晶粒
をランダム化することが必要である。発明者らは種々の
実験により、仕上圧延中において加工−再結晶を2回以
上繰り返すことにより、コロニー内の結晶粒がランダム
化することを見出した。このような仕上圧延中において
加工−再結晶を2回以上、繰り返すためには、仕上圧延
機のパス間で再結晶を起こす必要がある。通常の熱間圧
延工程ではパス間の時間が短いため、パス間で再結晶を
起こすのは困難である。しかしながら、例えば仕上圧延
中に1パス空圧延することにより、パス間で再結晶が起
こる時間が確保され、仕上圧延中において加工−再結晶
を2回以上繰り返すことが可能となる。Incidentally, in order to randomize the colonies formed on the hot-rolled sheet in the ferrite region, it is necessary to randomize the crystal grains in the colonies. The inventors have found from various experiments that crystal grains in a colony are randomized by repeating processing-recrystallization twice or more during finish rolling. In order to repeat the processing and recrystallization twice or more during such finish rolling, it is necessary to cause recrystallization between passes of the finish rolling mill. Since the time between passes is short in a normal hot rolling process, it is difficult to cause recrystallization between passes. However, for example, by performing one-pass idle rolling during finish rolling, a time period during which recrystallization occurs between passes is ensured, and processing-recrystallization can be repeated twice or more during finish rolling.
【0019】(3) 熱延鋼板の平均コロニーサイズ 熱延鋼板の平均コロニーサイズもまた、この発明におい
て重要であり、冷延−焼鈍後の耐リジング性を改善する
ためは、熱延鋼板の平均コロニーサイズをを80μm 以下
にする必要がある。すなわち、詳細な機構は不明である
が熱延板にて平均コロニーサイズが80μm より大きい場
合は、たとえ鋼成分及び冷延−焼鈍条件を変化させて
も、優れた耐リジング性は得られない。なお、フェライ
ト域熱延板に形成されるコロニーをサイズを80μm 以下
にするためには、粗圧延の温度の低下および高圧下にて
行うことが有効であり、そのための粗圧延終了温度は11
00℃以下好ましくは1000℃以下である。また粗圧延時の
圧下率も重要であり好ましくは粗最終パスを25%以上の
圧下率にて行うことが好ましい。(3) Average Colony Size of Hot-Rolled Steel Sheet The average colony size of a hot-rolled steel sheet is also important in the present invention. In order to improve ridging resistance after cold rolling and annealing, the average The colony size must be less than 80μm. That is, although the detailed mechanism is unknown, when the average colony size of the hot-rolled sheet is larger than 80 μm, excellent ridging resistance cannot be obtained even if the steel composition and the conditions of cold rolling and annealing are changed. In order to reduce the size of the colonies formed on the hot-rolled sheet in the ferrite region to 80 μm or less, it is effective to perform the rough rolling at a reduced temperature and at a high pressure.
The temperature is not higher than 00 ° C, preferably not higher than 1000 ° C. The rolling reduction during rough rolling is also important, and it is preferable to perform the rough final pass at a rolling reduction of 25% or more.
【0020】(4) 熱延鋼板の平均結晶粒径 深絞り加工を施すような2ピース缶では、イヤリング性
が小さいこと、すなわち、深絞り加工後の耳発生が少な
いことが重要視される。このイヤリングが発生した部分
は缶の深絞り成形後に切り捨てる必要があるために、こ
のイヤリング性が大きいと、材料歩留まりが悪くなるば
かりか、場合によっては必要な成形高さが得られず、成
形品全体を破棄しなければならなくなる。したがって、
深絞り成形時に発生するイヤリングは極力小さいことが
望ましい。ところで、イヤリングの高さは冷延鋼板のr
値面内異方性:Δr(=(r0 +r90−r45)/2)
(r0 ,r90,r45はそれぞれ圧延方向に0°,90°,
45°方向のr値)と良い相関があり、Δr=0であれば
イヤリング高さは0になることが知られている。ここ
に、Δrを0に近づけるには、仕上げ圧延終了後、0.5
秒以内に熱延鋼帯の水冷を開始し、70℃/s以上の冷却速
度で急冷し、少なくとも750 ℃以下まで冷却して、熱延
板の結晶粒径を35μm 以下に微細化することにより、冷
延・焼鈍・更に調質圧延後の製品板のΔr値が小さくな
ることを見いだした。したがって、この発明では熱延板
の平均結晶粒径を35μm 以下とし、熱間圧延の際は、後
述するように仕上げ圧延終了後、0.5 秒以内に熱延鋼帯
の水冷を開始し、70℃/s以上の冷却速度で急冷し、少な
くとも750 ℃以下まで冷却することが好ましい。(4) Average Crystal Grain Size of Hot-Rolled Steel Sheet In a two-piece can subjected to deep drawing, it is important that earring properties are small, that is, ears after deep drawing are small. Since the part where this earring has occurred must be cut off after deep drawing of the can, if this earring is large, not only the material yield will deteriorate, but also in some cases, the required molding height will not be obtained, and the molded product will not be obtained. You have to destroy everything. Therefore,
It is desirable that earrings generated during deep drawing are as small as possible. By the way, the height of the earring is r
Value in-plane anisotropy: Δr (= (r 0 + r 90 −r 45 ) / 2)
(R 0 , r 90 , r 45 are 0 °, 90 °,
(R value in the 45 ° direction), and it is known that if Δr = 0, the earring height becomes zero. Here, in order to make Δr close to 0, 0.5 g after finish rolling is completed.
Start water cooling of the hot-rolled steel strip within seconds, quench at a cooling rate of 70 ° C / s or more, cool to at least 750 ° C or less, and refine the crystal grain size of the hot-rolled sheet to 35 μm or less. It was also found that the Δr value of the product sheet after cold rolling, annealing and further temper rolling was reduced. Therefore, in the present invention, the average crystal grain size of the hot-rolled sheet is set to 35 μm or less, and during hot rolling, water-cooling of the hot-rolled steel strip is started within 0.5 seconds after finishing rolling as described later, and the temperature is reduced to 70 ° C. It is preferable to rapidly cool at a cooling rate of at least 750 ° C./s to at least 750 ° C. or less.
【0021】(5) 熱間圧延工程 スラブ加熱温度は、省エネルギー化のためには、1200℃
以下が好ましく、より好ましくは1100℃以下である。ま
た、粗圧延を(Ar3 変態点+150 ℃)〜(Ar3変態点+5
0℃)の温度範囲で終了することが好ましい。これは、
この温度範囲より低い温度で粗圧延した場合には、その
後に、後述する好適な冷却方法を採っても熱延板は粗大
な結晶粒となり、コロニーの微細化が達成されないため
に目的の耐リジング性が得られなくなる。一方、この範
囲を超える高温で粗圧延をすると、圧延ロール寿命の短
命化につながる。したがって、圧延終了温度範囲を(Ar
3変態点+150 ℃)〜(Ar3 変態点+50℃)とすること
が好ましい。また、コロニー内の結晶粒をランダム化す
るためには、仕上圧延中において加工−再結晶を繰り返
すことが重要であるので、仕上圧延中の高温域で高圧下
率圧延を施すことが好ましい。また、製品板のΔrを小
さくするためには、仕上げ圧延終了後、0.5 秒以内に熱
延鋼帯の水冷を開始し、70℃/s以上の冷却速度で急冷
し、少なくとも750 ℃以下まで冷却する必要がある。仕
上げ圧延終了から水冷開始までの空冷時間が0.5 秒を超
えた場合、あるいは冷却速度が70℃/sより小さい場合
は、結晶粒成長が進行し、結晶粒の微細化が達成されな
い。巻取温度は、650 ℃以上800 ℃以下とするのが好ま
しい。コロニー内の結晶粒をランダム化するためには、
巻取温度を高くして、高温域である程度以上の時間、保
持させる必要があり、これにより圧延加工組織が再結晶
することでコロニー内の結晶粒がランダム化する。巻取
温度が650 ℃より低い場合には、再結晶が進行せず、結
晶粒のランダム化が達成されない。一方、巻取温度が80
0 ℃を超えると、巻取後のスケール成長が著しくなり酸
洗性が低下する他、結晶粒が以上に粗大化して材質が劣
化したり、耐肌荒れ性が劣化する等の不具合が生じるた
め上限を800 ℃とした。なお、熱延板の再結晶を促進す
る仕上圧延後段強圧下は、耐リジング性改善には有効な
手段である。また、仕上圧延時に潤滑圧延を施すこと
は、圧延組織の均一化、圧延荷重の減少に有効であり、
この発明を阻害するものではない。(5) Hot Rolling Step The slab heating temperature is 1200 ° C. for energy saving.
Or less, more preferably 1100 ° C. or less. Further, the rough rolling (Ar 3 transformation point +150 ℃) ~ (Ar 3 transformation point + 5
(0 ° C.). this is,
When the rough rolling is performed at a temperature lower than this temperature range, the hot rolled sheet becomes coarse crystal grains even if a suitable cooling method described later is employed, and the desired ridging resistance is not obtained since the miniaturization of colonies is not achieved. The property cannot be obtained. On the other hand, when rough rolling is performed at a high temperature exceeding this range, the life of the rolling rolls is shortened. Therefore, the rolling end temperature range (Ar
It is preferred that 3 transformation point +150 ° C.) ~ and (Ar 3 transformation point + 50 ° C.) to. Further, in order to randomize the crystal grains in the colony, it is important to repeat the processing and recrystallization during the finish rolling. Therefore, it is preferable to perform the high-pressure reduction in a high temperature region during the finish rolling. In addition, in order to reduce the Δr of the product sheet, water cooling of the hot-rolled steel strip is started within 0.5 seconds after the finish rolling, quenched at a cooling rate of 70 ° C / s or more, and cooled to at least 750 ° C or less. There is a need to. If the air cooling time from the end of finish rolling to the start of water cooling exceeds 0.5 seconds, or if the cooling rate is less than 70 ° C./s, the crystal grain growth proceeds, and the crystal grains cannot be refined. The winding temperature is preferably set to 650 ° C or higher and 800 ° C or lower. To randomize the grains in a colony,
It is necessary to raise the winding temperature and hold the film in a high temperature region for a certain period of time or more, whereby the crystal structure in the colony is randomized by recrystallization of the rolled structure. If the winding temperature is lower than 650 ° C., recrystallization does not proceed, and randomization of crystal grains cannot be achieved. On the other hand, the winding temperature is 80
If the temperature exceeds 0 ° C., the scale growth after winding will be remarkable, and the pickling property will be reduced. In addition, the crystal grains will become coarser and the material will be deteriorated, and the rough surface resistance will be deteriorated. Was set to 800 ° C. It is to be noted that strong rolling after finish rolling which promotes recrystallization of a hot-rolled sheet is an effective means for improving ridging resistance. In addition, performing lubrication rolling during finish rolling is effective in uniformizing the rolling structure and reducing the rolling load,
It does not hinder the invention.
【0022】(6) 冷間圧延工程 この工程は、高いr値を得るために必須であり、冷延圧
下率は80〜95%とすることが好ましい。 (7) 連続焼鈍工程 連続焼鈍は、再結晶終了温度以上の焼鈍温度か必要であ
るが、焼鈍温度が高すぎると結晶粒が異常に粗大化し、
加工後の肌荒れが大きくなる他、缶用鋼板等の薄物材で
は炉内破断やバックリング発生の危険が大きくなるため
に750 ℃を上限とすることが望ましい。(6) Cold Rolling Step This step is essential for obtaining a high r-value, and the cold rolling reduction is preferably set to 80 to 95%. (7) Continuous annealing step Continuous annealing requires an annealing temperature equal to or higher than the recrystallization end temperature, but if the annealing temperature is too high, the crystal grains abnormally coarsen,
The upper limit of the temperature is desirably 750 ° C., because the surface roughness after processing becomes large, and thin materials such as steel plates for cans have a high risk of breakage in the furnace and occurrence of buckling.
【0023】(8) 調質圧延 調質圧延の圧下率は、鋼板の調質度により随時決定され
るが、ストレッチャーストレインの発生を防止するため
には、0.5 %異常の圧下率で圧延する必要がある。一
方、40%を超える圧下率で圧延すると鋼板が過度に硬質
化して、加工性が低下する他、r値の低下(深絞り性の
劣化)が起こるために、その上限を40%とすることが好
ましい。(8) Temper Rolling The reduction ratio of the temper rolling is determined at any time according to the degree of tempering of the steel sheet. In order to prevent the occurrence of stretcher strain, rolling is performed at an abnormal reduction ratio of 0.5%. There is a need. On the other hand, if the rolling is performed at a rolling reduction exceeding 40%, the steel sheet becomes excessively hard and the workability is reduced, and the r-value is reduced (depth drawability is deteriorated). Is preferred.
【0024】[0024]
【実施例】表1に示す組成になる高をスラブを1200℃に
加熱−均熱後、表2に示す熱延条件にて板厚2.5 mmの熱
延鋼帯にした。このとき得られた熱延鋼板のコロニー内
の方位集中度も表2に併せて示す。引き続き冷間圧延に
て板厚0.25mmの冷延鋼帯とし、750 ℃−20s の再結晶焼
鈍を施した。得られた冷延鋼板の材料特性を調査した。
引張特性はJIS 5号引張試験片を使用して測定した。ま
た、r値は15%引張予歪を与えた後、3点法にて測定
し、L方向(圧延方向)、D(圧延方向に45度方向)及
びC方向(圧延方向に90度方向)の平均値及びr値の異
方性を、それぞれ次式により平均r値及びΔrとして求
めた。 平均r値=(r0 +2r45+r90)/4 r値面内異方性=(r0 +r90−r45)/2) (r0 ,r90,r45はそれぞれ圧延方向に0°,90°,
45°方向のr値) また、耐リジング性は、リジング評価指数を用いて判定
し、JIS 5号引張試験片に加工した鋼板に15%引張歪を
与えたものを目視により評価して求めた。リジング評価
指数が2以下のものは実用上問題のないリジングレベル
である。最終製品の材料特性を表2に示す。この発明に
従い製造した冷延鋼板用素材は、冷延鋼板に加工した場
合に、比較例に比べ優れた耐リジング性と深絞り性とを
有することがわかる。EXAMPLE A slab was heated to 1200 ° C. and heated to 1200 ° C. to obtain the composition shown in Table 1, and then a hot-rolled steel strip having a thickness of 2.5 mm was formed under the hot rolling conditions shown in Table 2. Table 2 also shows the degree of orientation concentration in the colony of the hot-rolled steel sheet obtained at this time. Subsequently, a cold-rolled steel strip having a thickness of 0.25 mm was formed by cold rolling and subjected to recrystallization annealing at 750 ° C. for 20 seconds. The material properties of the obtained cold rolled steel sheet were investigated.
Tensile properties were measured using JIS No. 5 tensile test pieces. The r value is measured by the three-point method after 15% tensile prestrain is applied, and the L direction (rolling direction), D (45 degree direction in rolling direction) and C direction (90 degree direction in rolling direction) Were determined as the average r value and Δr by the following formulas, respectively. Average r value = (r 0 + 2r 45 + r 90 ) / 4 In-plane anisotropy of r value = (r 0 + r 90 -r 45 ) / 2) (r 0 , r 90 , and r 45 are each 0 ° in the rolling direction. , 90 °,
(R value in the 45 ° direction) The ridging resistance was determined using a ridging evaluation index, and a steel sheet processed into a JIS No. 5 tensile test piece, which was given a 15% tensile strain, was visually evaluated. . Those having a ridging evaluation index of 2 or less are ridging levels having no practical problem. Table 2 shows the material properties of the final product. It can be seen that the material for a cold-rolled steel sheet manufactured according to the present invention, when processed into a cold-rolled steel sheet, has superior ridging resistance and deep drawability as compared with Comparative Examples.
【0025】[0025]
【表1】 [Table 1]
【0026】[0026]
【表2】 [Table 2]
【0027】[0027]
【発明の効果】この発明によれば、熱延鋼板のコロニー
を微細化し、かつコロニー内の方位集中度を限定するこ
とにより、従来よりも格段に優れた耐リジング性と深絞
り性とを有する缶用冷延鋼板の製造が可能となる。な
お、この発明の鋼板は、すずめっき鋼板及びティンフリ
ーテチールとしてのみでなく、亜鉛めっき、Niめっき及
び塗油鋼板としても用いることができ、また、その用途
適用範囲は深絞り加工等の加工を施す食缶及び飲料缶等
の各種金属缶のみならず、乾電池内装缶等から各種家電
・電位部品及び自動車部品等までと、幅広い範囲での活
用が期待できる。According to the present invention, a colony of a hot-rolled steel sheet is miniaturized and the degree of azimuth concentration in the colony is limited, so that the ridging resistance and the deep drawability are far superior to those of the prior art. Production of cold-rolled steel sheets for cans becomes possible. The steel sheet of the present invention can be used not only as a tin-plated steel sheet and tin-free tetyl, but also as a zinc-plated, Ni-plated and oil-coated steel sheet. In addition to various metal cans such as food cans and beverage cans, which can be used for a variety of applications, it can be expected to be used in a wide range of applications, from interior cans for dry batteries to various home appliances, potential parts, and automobile parts.
【図1】耐リジング性に及ぼす熱延鋼板のコロニー内の
方位集中度及びコロニーサイズの影響を示す図である。FIG. 1 is a diagram showing the influence of the orientation concentration and colony size in a colony of a hot-rolled steel sheet on ridging resistance.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 坂田 敬 千葉県千葉市中央区川崎町1番地 川崎製 鉄株式会社技術研究所内 (72)発明者 小原 隆史 千葉県千葉市中央区川崎町1番地 川崎製 鉄株式会社技術研究所内 (72)発明者 久々湊 英雄 千葉県千葉市中央区川崎町1番地 川崎製 鉄株式会社千葉製鉄所内 ──────────────────────────────────────────────────の Continuing from the front page (72) Inventor Takashi Sakata 1 Kawasaki-cho, Chuo-ku, Chiba City, Chiba Prefecture Inside the Technical Research Institute of Kawasaki Steel Co., Ltd. (72) Inventor Takashi Ohara 1 Kawasaki-cho, Chuo-ku, Chiba City, Chiba Prefecture Kawasaki (72) Inventor Hideo Kuguminato 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Chiba Works
Claims (3)
組成よりなり、かつ平均結晶粒径dが35μm 以下、平均
コロニーサイズが80μm 以下及び下記に示すコロニー内
の方位集中度Sが0.8 以下であることを特徴とする冷延
−焼鈍後の耐リジング性及び深絞り性に優れる缶用鋼板
用素材。 記 S=X20゜/X30゜ ここに、 X30゜:隣接する結晶粒間の方位差が30°以内のコロニ
ー面積 X20゜:X30゜のうち、隣接する結晶粒間の方位差が20
°以内のコロニー面積1. C: 0.0005 to 0.0150 wt%, Si: 0.10 wt% or less, Mn: 0.1 to 0.6 wt%, P: 0.02 wt% or less, S: 0.02 wt% or less, Al: 0.015 to 0.15 wt% and N: 0.02 wt% or less as a basic component, the balance being composed of Fe and unavoidable impurities, and having an average crystal grain size d of 35 μm or less, an average colony size of 80 μm or less, and a degree of orientation concentration in the colony shown below. A material for a steel sheet for cans having excellent ridging resistance and deep drawability after cold rolling and annealing, wherein S is 0.8 or less. Here serial S = X 20 ° / X 30 °, X 30 °: adjacent colony area X 20 ° misorientation is within 30 ° between the crystal grains: among X 30 °, the orientation difference between adjacent grains Is 20
° Colony area within °
記載の冷延−焼鈍後の耐リジング性及び深絞り性に優れ
る缶用鋼板用素材。2. The composition according to claim 1, further comprising at least one of 0.001 to 0.02% by weight of Ti and 0.001 to 0.02% by weight of Nb in addition to the basic components.
A steel sheet material for cans having excellent ridging resistance and deep drawability after cold rolling and annealing as described.
−焼鈍後の耐リジング性及び深絞り性に優れる缶用鋼板
用素材。3. The can according to claim 1, which further comprises B: 0.0001 to 0.0030% by weight in addition to the basic component, which is excellent in ridging resistance and deep drawability after cold rolling and annealing. Material for steel plate.
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JP25609296A JP3852138B2 (en) | 1996-09-27 | 1996-09-27 | Method for producing a steel plate material for cans having excellent ridging resistance and deep drawability after cold rolling and annealing |
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JP25609296A JP3852138B2 (en) | 1996-09-27 | 1996-09-27 | Method for producing a steel plate material for cans having excellent ridging resistance and deep drawability after cold rolling and annealing |
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Publication Number | Publication Date |
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JPH10102191A true JPH10102191A (en) | 1998-04-21 |
JP3852138B2 JP3852138B2 (en) | 2006-11-29 |
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JP25609296A Expired - Fee Related JP3852138B2 (en) | 1996-09-27 | 1996-09-27 | Method for producing a steel plate material for cans having excellent ridging resistance and deep drawability after cold rolling and annealing |
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2008179877A (en) * | 2006-03-16 | 2008-08-07 | Jfe Steel Kk | Cold rolled steel sheet with excellent non-earing property, and its manufacturing method |
WO2008102006A1 (en) * | 2007-02-23 | 2008-08-28 | Corus Staal Bv | Packaging steel, method of producing said packaging steel and its use |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102605250B (en) * | 2012-03-27 | 2014-01-15 | 首钢总公司 | Vehicle steel plate and production method thereof |
-
1996
- 1996-09-27 JP JP25609296A patent/JP3852138B2/en not_active Expired - Fee Related
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2008179877A (en) * | 2006-03-16 | 2008-08-07 | Jfe Steel Kk | Cold rolled steel sheet with excellent non-earing property, and its manufacturing method |
EP2806046A1 (en) * | 2006-03-16 | 2014-11-26 | JFE Steel Corporation | Cold-rolled steel sheet, method of producing the same, battery, and method of producing the same |
WO2008102006A1 (en) * | 2007-02-23 | 2008-08-28 | Corus Staal Bv | Packaging steel, method of producing said packaging steel and its use |
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JP3852138B2 (en) | 2006-11-29 |
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