JPH06306535A - Surface treated original sheet for di can excellent in necked-in property and its production - Google Patents

Abstract

PURPOSE:To provide a surface treated original sheet for a DI can excellent in necked-in properties and to provide its producing method. CONSTITUTION:This surface treated original sheet for a DI can excellent in necked-in properties is a one having a compsn. contg. 0.0005 to 0.0700% C, <=0.30% Si, 0.05 to l.00% Mn, <=0.030% P, <=0.025% S, 0.002 to 0.100% sol.Al, <=0.0100% N, 0 to (0.0010+1.8XN%)% B and 0 to 0.050% of one or to kinds of Nb and Ti, and the balance iron with inevitable impurities, and in which Y. P (3% BH) is regulated to 34 to <39kgf/m<2> and Y. P (50% BH) is regulated to <=62kgf/mm<2>. This surface treated original sheet is produced in ordinary continuous annealing equipment and overaging treating equipment by a continuous annealing method, a box annealing method and an extremely compact continuous annealing method.

Description

【発明の詳細な説明】Detailed Description of the Invention

【０００１】[0001]

【産業上の利用分野】本発明は錫メッキが施されるＤＩ
缶用表面処理原板において、缶のネックドイン性に優れ
たＤＩ缶用表面処理原板及び製造方法に関するものであ
る。FIELD OF THE INVENTION The present invention is a tin-plated DI.
TECHNICAL FIELD The present invention relates to a surface-treated original plate for a DI can which is excellent in the necked-in property of the can, and a method for producing the same.

【０００２】尚、本明細書において使用する略語は下記
の意味を有する。 Ｇ．Ｓｎｏ：原板の結晶粒度番号 Ｙ．Ｐ( 3%ＢＨ):伸び率3%の追加圧延予歪後ＢＨ熱処理
を行った後のＹ．Ｐ Ｙ．Ｐ(50%ＢＨ):伸び率50% の追加圧延予歪後ＢＨ熱処
理を行った後のＹ．Ｐ ＢＨ熱処理： 200℃×10min の熱処理The abbreviations used in this specification have the following meanings. G. Sno: Crystal grain size number of original plate Y. P (3% BH): Y.I. P Y. P (50% BH): Y.I. P BH heat treatment: heat treatment of 200 ℃ × 10min

【０００３】[0003]

【従来の技術】錫メッキが施されるＤＩ缶用表面処理原
板は、過去においては、特開昭６１−２４３１２４号公
報、特開昭５３−４８９１３号公報に示されるような箱
焼鈍法で製造されたイヤリング性を改良した等軸粒のア
ルミキルド鋼や古くからある延伸粒のアルミキルド鋼が
適用され、テンパー度が１〜２（以下Ｔ−１，Ｔ−２と
記す）程度の軟質で非時効性の鋼板であった。その後、
鋼板の板厚を減少させ、ＤＩ缶の軽量化が進められた。
この軽量化を行うに当たり、ＤＩ缶のボトム部の内圧に
対する耐圧強度不足を補うため、従来から製造されてい
たＡｌ−Ｋ鋼を連続焼鈍で製造するＴ−４ＣＡと称され
る硬質でＢＨ性のある鋼板に切り替えられ適用されてき
た。2. Description of the Related Art A tin-plated surface-treated original plate for a DI can has been manufactured in the past by a box annealing method as disclosed in JP-A-61-243124 and JP-A-53-48913. Equipped with equiaxed grain aluminum-killed steel with improved earring properties and long-term drawn grain aluminum-killed steel, which is soft and has a temper degree of 1 to 2 (hereinafter referred to as T-1 and T-2) and is not aged. It was a steel plate with good properties. afterwards,
The thickness of the steel sheet was reduced and the weight of the DI can was reduced.
In order to make up for this weight reduction, in order to compensate for the lack of pressure strength against the internal pressure of the bottom part of the DI can, a hard and BH-type steel called T-4CA which is manufactured by continuous annealing of Al-K steel which has been conventionally manufactured is used. It has been switched to a certain steel plate and applied.

【０００４】最近では、ＤＩ缶の軽量化はより一層の進
展が望まれている一方、ＤＩ缶のＴＯＰ部（ネックドイ
ン部）の径は、缶蓋に使用されるＡｌ板のコストダウン
のため、小径化が行われ、多段ネックドイン加工が施さ
れるようになり、ついには、４段ネックドイン加工が採
用されはじめた。しかし、現状のＤＩ缶用素材として供
給されているＴ−４ＣＡでは、缶の耐圧力は充分である
が、例えば缶蓋の径が２０４φ即ち（２＋４／１６）φ
吋のような小径化時にはネックドイン率がより厳しくな
る４段ネックドイン加工を行わねばならないが、しわが
発生するという問題があり、進展が停滞している状況に
ある。Recently, it has been desired to further reduce the weight of DI cans. On the other hand, the diameter of the TOP part (necked-in part) of DI cans is reduced because of the cost reduction of the Al plate used for the can lid. With the reduction in diameter, multi-step necked-in processing has come to be applied, and finally, 4-step necked-in processing has begun to be adopted. However, with T-4CA which is currently supplied as a material for DI cans, the pressure resistance of the cans is sufficient. For example, the diameter of the can lid is 204φ, that is, (2 + 4/16) φ.
A 4-step necked-in process, which makes the necked-in rate more severe when making the diameter smaller like a bowl, has to be performed, but there is a problem that wrinkles occur, and the progress is stagnant.

【０００５】以上述べたように、より優れた金属容器と
してのＤＩ缶を作るには、まだ、充分な特性を持ったＤ
Ｉ缶用の表面処理原板はないのである。この問題を解決
するための、ネックドイン性に優れたＤＩ缶用表面処理
原板ならびに製造方法の提供が強く望まれている。As mentioned above, in order to make a DI can as a better metal container, D having sufficient characteristics is still available.
There is no surface-treated original plate for I cans. It has been strongly desired to provide a surface-treated original plate for DI can excellent in necked-in property and a production method for solving this problem.

【０００６】[0006]

【発明が解決しようとする課題】このような現状から本
発明が解決しようとする課題は、現状の耐圧強度を維持
し、ネックドイン性に優れたＤＩ缶用表面処理原板なら
びに製造方法を提供することである。The problem to be solved by the present invention is to provide a surface-treated original plate for a DI can excellent in necked-in property while maintaining the current pressure resistance and a manufacturing method. Is.

【０００７】[0007]

【課題を解決するための手段】本発明者等は、上記課題
を解決するために、ＤＩ缶の現状レベルの耐圧強度と優
れたネックドイン性を両立させ得る鋼板特性が有り得る
のか、また、達成手段は何か等について種々検討し、ネ
ックドイン性に優れたＤＩ缶用表面処理原板を初めて見
いだしたものである。更に鋼板の製造法についても種々
検討し、その製造方法を見いだしたものである。In order to solve the above-mentioned problems, the inventors of the present invention have the steel plate characteristics capable of satisfying both the current level of pressure resistance of DI cans and excellent necked-in properties, and the means for achieving the same. This is the first time to find a surface-treated original plate for a DI can that is excellent in necked-in property by conducting various studies on what is. Furthermore, various studies were conducted on the manufacturing method of the steel sheet, and the manufacturing method was found.

【０００８】本発明の要旨は下記の通りである。 (1) 重量％で、Ｃ：０．０００５〜０．０７００％、Ｓ
ｉ：≦０．３０％、Ｍｎ：０．０５〜１．００％、
Ｐ ：≦０．０３０％、Ｓ：≦０．０２５％、
sol.Ａｌ：０．００２〜０．１００％、Ｎ：≦
０．０１００％、Ｂ：０〜（０．００１０＋１．８×Ｎ
％）％、Ｎｂ及びＴｉの１種または２種：０〜０．０５
０％、残部不可避的不純物及び鉄よりなり、Ｙ．Ｐ（３
％ＢＨ）が３４kgf/mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ
（５０％ＢＨ）が６２kgf/mm² 以下であることを特徴と
するネックドイン性に優れたＤＩ缶用表面処理原板。The gist of the present invention is as follows. (1)% by weight, C: 0.0005 to 0.0700%, S
i: ≦ 0.30%, Mn: 0.05 to 1.00%,
P: ≤0.030%, S: ≤0.025%,
sol.Al: 0.002 to 0.100%, N: ≤
0.0100%, B: 0- (0.0010 + 1.8 × N
%)%, One or two of Nb and Ti: 0 to 0.05
0%, the balance consisting of inevitable impurities and iron, Y. P (3
% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P
(50% BH) is 62 kgf / mm ² or less, and a surface-treated original plate for DI can having excellent necked-in properties.

【０００９】(2) 請求項(1) の記載の表面処理原板にお
いて、Ｇ．Ｓｎｏが９．０以上であることを特徴とする
フランジ加工性の良好なネックドイン性に優れたＤＩ缶
用表面処理原板の製造方法。(2) In the surface-treated original plate according to claim (1), G. A method for producing a surface-treated original plate for a DI can having a good flange formability and an excellent necked-in property, wherein Sno is 9.0 or more.

【００１０】(3) 重量％で、Ｃ：０．０００５〜０．０
０６０％、Ｓｉ：≦０．３０％、Ｍｎ：０．０５〜１．
００％、 Ｐ ：≦０．０３０％、Ｓ：≦０．０２
５％、 sol.Ａｌ：０．００２〜０．１０
０％、Ｎ：≦０．０１００％、Ｂ：０〜（０．００１０
＋１．８×Ｎ％）％、Ｎｂ及びＴｉの１種または２種：
０〜０．０３％、残部不可避的不純物及び鉄よりなる鋳
片を、熱間圧延を行い熱延鋼帯とし、８５〜９５％の冷
間圧延率で冷間圧延を行い、連続焼鈍法で再結晶温度〜
８３０℃で再結晶焼鈍を行い、室温まで冷却し、鋼板中
の固溶Ｃ量を５ppm 未満とした後、調質圧延で５％以上
１５％以下の歪を付与し、鋼板のＹ．Ｐ（３％ＢＨ）を
３４kgf/mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５０％Ｂ
Ｈ）を６２kgf/mm² 以下に調整することを特徴とするネ
ックドイン性に優れたＤＩ缶用表面処理原板の製造方
法。(3) C: 0.0005-0.0 by weight%
060%, Si: ≤ 0.30%, Mn: 0.05-1.
00%, P: ≤0.030%, S: ≤0.02
5%, sol.Al: 0.002-0.10
0%, N: ≤ 0.0100%, B: 0- (0.0010
+ 1.8 × N%)%, one or two of Nb and Ti:
A slab consisting of 0 to 0.03%, the balance unavoidable impurities and iron is hot-rolled to form a hot-rolled steel strip, which is cold-rolled at a cold-rolling rate of 85 to 95% by a continuous annealing method. Recrystallization temperature ~
After performing recrystallization annealing at 830 ° C., cooling to room temperature and setting the amount of solute C in the steel sheet to less than 5 ppm, strain of 5% or more and 15% or less is imparted by temper rolling, and Y. P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P (50% B
H) is adjusted to 62 kgf / mm ² or less, and a method for producing a surface-treated original plate for a DI can having excellent necked-in properties.

【００１１】(4) 重量％で、Ｃ：０．００２０〜０．０
０６０％、Ｓｉ：≦０．３０％、Ｍｎ：０．０５〜１．
００％、 Ｐ ：≦０．０３０％、Ｓ：≦０．０２
５％、 sol.Ａｌ：０．００２〜０．１０
０％、Ｎ：≦０．０１００％、Ｂ：０〜（０．００１０
＋１．８×Ｎ％）％、Ｎｂ及びＴｉの１種または２種：
０〜０．０１％、残部不可避的不純物及び鉄よりなる鋳
片を、熱間圧延を行い熱延鋼帯とし、８５〜９５％の冷
間圧延率で冷間圧延を行い、連続焼鈍法で再結晶温度〜
８３０℃で再結晶焼鈍を行い、室温まで冷却し、鋼板中
の固溶Ｃ量を５ppm 〜４０ppm 残留せしめ、その後、調
質圧延でドライ調質圧延が可能な伸び率で７％未満の歪
を付与し、鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以
上３９kgf/mm² 未満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/
mm² 以下に調整することを特徴とするネックドイン性に
優れたＤＩ缶用表面処理原板の製造方法。(4) C: 0.0020-0.0 by weight%
060%, Si: ≤ 0.30%, Mn: 0.05-1.
00%, P: ≤0.030%, S: ≤0.02
5%, sol.Al: 0.002-0.10
0%, N: ≤ 0.0100%, B: 0- (0.0010
+ 1.8 × N%)%, one or two of Nb and Ti:
A slab consisting of 0 to 0.01% and the balance unavoidable impurities and iron is hot-rolled to form a hot-rolled steel strip, which is cold-rolled at a cold-rolling rate of 85 to 95% by a continuous annealing method. Recrystallization temperature ~
Recrystallization annealing is performed at 830 ° C., cooling to room temperature is made to leave a solid solution C amount of 5 ppm to 40 ppm in the steel sheet, and then straining of less than 7% is possible in the temper rolling for elongation tempering. Y. P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. 62 kgf / P (50% BH)
A method for producing a surface-treated original plate for a DI can having excellent necked-in properties, which is characterized by adjusting the size to ² mm ² or less.

【００１２】(5) 請求項３の記載の方法において、熱間
圧延時に８９０℃以上好ましくは９００℃以上で仕上げ
熱延を行い熱延鋼帯とすることを特徴とするＧ．Ｓｎ
ｏ：９．０以上のフランジ加工性の良好なネックドイン
性に優れたＤＩ缶用表面処理原板の製造方法。(5) In the method according to claim 3, G. characterized in that hot rolling is performed by finish hot rolling at 890 ° C. or higher, preferably 900 ° C. or higher during hot rolling. Sn
o: A method for producing a surface-treated original plate for a DI can having a flanged workability of 9.0 or more and excellent necked-in properties.

【００１３】(6) 重量％で、Ｃ：０．０１００〜０．０
７００％、Ｓｉ：≦０．３０％、Ｍｎ：０．０５〜１．
００％、 Ｐ ：≦０．０３０％、Ｓ：≦０．０２
５％、 sol.Ａｌ：０．００２〜０．１０
０％、Ｎ：≦０．０１００％、Ｂ：０〜（０．００１０
＋１．８×Ｎ％）％、残部不可避的不純物及び鉄よりな
る鋳片を、熱間圧延を行い熱延鋼帯とし、８５〜９５％
の冷間圧延率で冷間圧延を行い、連続焼鈍法で再結晶温
度〜８３０℃で再結晶焼鈍を行い、その後、３００〜５
５０℃で２０sec 以上の過時効処理を行い、室温まで冷
却し、鋼板中の固溶Ｃ量を５ppm 〜２０ppm と低減し、
その後、調質圧延で伸び率で２％以上１５％以下の歪を
付与し、鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上
３９kgf/mm² 未満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm
²以下に調整することを特徴とするネックドイン性に優
れたＤＩ缶用表面処理原板の製造方法。(6) C: 0.0100-0.0% by weight
700%, Si: 0.30%, Mn: 0.05-1.
00%, P: ≤0.030%, S: ≤0.02
5%, sol.Al: 0.002-0.10
0%, N: ≤ 0.0100%, B: 0- (0.0010
+ 1.8 × N%)%, the slab consisting of the balance unavoidable impurities and iron is hot-rolled into a hot-rolled steel strip, which is 85-95%
Cold rolling is performed at a cold rolling rate of No. 3, recrystallization annealing is performed at a recrystallization temperature of 830 ° C. by a continuous annealing method, and then 300 to 5
Perform overaging treatment for 20 seconds or more at 50 ° C, cool to room temperature, and reduce the amount of dissolved C in the steel sheet to 5ppm to 20ppm.
Then, a strain of 2% or more and 15% or less in elongation rate is applied by temper rolling, and the Y. P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P (50% BH) is 62 kgf / mm
^A method for producing a surface-treated original plate for a DI can excellent in necked-in property, which is adjusted to ² or less.

【００１４】(7) 重量％で、Ｃ：０．０００５〜０．０
７００％、Ｓｉ：≦０．３０％、Ｍｎ：０．０５〜１．
００％、 Ｐ ：≦０．０３０％、Ｓ：≦０．０２
５％、 sol.Ａｌ：０．００２〜０．１０
０％、Ｎ：≦０．０１００％、Ｂ：０〜（０．００１０
＋１．８×Ｎ％）％、Ｎｂ及びＴｉの１種または２種：
０〜０．０３％、残部不可避的不純物及び鉄よりなる鋳
片を、熱間圧延を行い熱延鋼帯とし、８５〜９５％の冷
間圧延率で冷間圧延を行い、箱焼鈍法で再結晶温度〜７
５０℃で再結晶焼鈍を行い、室温まで冷却し、その後、
調質圧延で伸び率で５％以上１５％以下の歪を付与し、
鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上３９kgf/
mm²未満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm² 以下に
調整することを特徴とするネックドイン性に優れたＤＩ
缶用表面処理原板の製造方法。(7) C: 0.0005-0.0 by weight%
700%, Si: 0.30%, Mn: 0.05-1.
00%, P: ≤0.030%, S: ≤0.02
5%, sol.Al: 0.002-0.10
0%, N: ≤ 0.0100%, B: 0- (0.0010
+ 1.8 × N%)%, one or two of Nb and Ti:
A slab consisting of 0 to 0.03%, the balance unavoidable impurities and iron is hot-rolled to form a hot-rolled steel strip, which is cold-rolled at a cold-rolling rate of 85 to 95% by a box annealing method. Recrystallization temperature ~ 7
Perform recrystallization annealing at 50 ° C., cool to room temperature, then
Distortion of 5% or more and 15% or less in elongation rate is applied by temper rolling,
Y. P (3% BH) is 34 kgf / mm ² or more 39 kgf /
less than mm ^2, Y. DI with excellent necked-in property characterized by adjusting P (50% BH) to 62 kgf / mm ² or less
Manufacturing method of surface-treated original plate for can.

【００１５】(8) 重量％で、Ｃ：０．０００５〜０．０
０６０％、Ｓｉ：≦０．３０％、Ｍｎ：０．０５〜１．
００％、 Ｐ ：≦０．０３０％、Ｓ：≦０．０２
５％、 sol.Ａｌ：０．００２〜０．１０
０％、Ｎ：≦０．０１００％、Ｂ：０〜（０．００１０
＋１．８×Ｎ％）％、Ｎｂ及びＴｉの１種または２種：
０〜０．０５０％、残部不可避的不純物及び鉄よりなる
鋳片を、熱間圧延を行い熱延鋼帯とし、８５〜９５％の
冷間圧延率で冷間圧延を行い、その後再結晶焼鈍をする
に際し、５００℃以上の温度域を１００〜２５００℃／
ｓの加熱速度で再結晶温度〜９２０℃に加熱し、その温
度域で０〜１０sec 滞在せしめて再結晶焼鈍を行い、室
温まで冷却し、その後、調質圧延で伸び率で１５％以下
の歪を付与し、鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm
² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５０％ＢＨ）を６２
kgf/mm² 以下に調整することを特徴とするＧ．Ｓｎｏ：
９．０以上のフランジ加工性の良好なネックドイン性に
優れたＤＩ缶用表面処理原板の製造方法。(8) C: 0.0005-0.0 by weight%
060%, Si: ≤ 0.30%, Mn: 0.05-1.
00%, P: ≤0.030%, S: ≤0.02
5%, sol.Al: 0.002-0.10
0%, N: ≤ 0.0100%, B: 0- (0.0010
+ 1.8 × N%)%, one or two of Nb and Ti:
A slab consisting of 0 to 0.050%, the balance unavoidable impurities and iron is hot rolled into a hot rolled steel strip, cold rolled at a cold rolling rate of 85 to 95%, and then recrystallized annealing. The temperature range of 500 ° C or higher is 100 to 2500 ° C /
It is heated to a recrystallization temperature of 920 ° C. at a heating rate of s, allowed to stay in that temperature range for 0 to 10 seconds, and recrystallized and annealed, cooled to room temperature, and then temper-rolled to obtain an elongation of 15% or less. Is added to the steel plate, and Y. 34 kgf / mm of P (3% BH)
² or more and less than 39 kgf / mm ² , Y. P (50% BH) is 62
G. characterized by adjusting to less than kgf / mm ² . Sno:
A method for producing a surface-treated original plate for a DI can having a flange workability of 9.0 or more and excellent necked-in properties.

【００１６】以下に本発明について詳細に述べる。本発
明者等は、先ず、一方で高い強度を維持することが求め
られ、もう一方でより軟質であることが求められると言
った相反することが要求されるＤＩ缶の現状レベルの耐
圧強度と優れたネックドイン性を両立させ得る鋼板特性
が有り得るのかについて検討し、可能性があることを見
いだした。以下に、両立させ得る考え方について説明す
る。The present invention will be described in detail below. The inventors of the present invention firstly required to maintain high strength on the one hand and, on the other hand, required to be softer on the other hand. We examined whether there is a steel sheet property that can achieve both excellent necked-in properties, and found that there is a possibility. Below, the idea which can be made compatible is explained.

【００１７】先ず、ネックドイン性を向上させるには、
どうすれば良いかと言うことについて検討を行った。Ｄ
Ｉ缶のネックドイン性を向上させるには、ネックドイン
加工時のネックドイン部の変形抵抗を下げる方法が容易
に思いつくことができる。本発明者等も、先ず最初に、
ＤＩ加工前のメッキ原板の強度を低下させる方法とし
て、従来適用されてきた箱焼鈍法によるＤＩ缶用メッキ
原板の適用の可能性を調査したが、耐圧強度が全く確保
できないと言う結果となり、従来の軟質なＤＩ缶用メッ
キ原板では適用できないことを改めて確認した。First, in order to improve the necked-in property,
I examined what to say. D
In order to improve the necked-in property of the I can, a method of lowering the deformation resistance of the necked-in portion during necked-in processing can be easily conceived. The present inventors also first of all,
As a method of reducing the strength of the original plating plate before DI processing, we investigated the possibility of applying the original plating plate for DI cans by the box annealing method that has been conventionally applied, but the result was that pressure resistance could not be secured at all. It was reconfirmed that this method cannot be applied to the soft plating plate for DI cans.

【００１８】そこで、ＤＩ缶の現状レベルの耐圧強度と
優れたネックドイン性を両立させ得る鋼板の可能性につ
いて検討した。このＤＩ缶の現状レベルの耐圧強度と優
れたネックドイン性を両立させ得る鋼板特性は、たしか
に、一方で高い強度が求められ、もう一方でより軟質で
あることが求められると言った相反することが要求され
ることはその通りであるが、本発明者等は、ＤＩ缶の耐
圧強度とネックドイン部の強度とは一体どのようなもの
であるのかについて検討した。従来は、上記の従来の軟
質なＤＩ缶用メッキ原板の調査結果にも示されるよう
に、ＤＩ缶の耐圧強度とネックドイン部の強度とは、原
板の強度に比例し、どちらも、原板強度が高いと高くな
る。従って、鋼板の強度上昇による軽量化と鋼板の軟質
化によるネックドイン性の向上は、両立しがたいと考え
られていた。Therefore, the possibility of a steel sheet which is compatible with the current level of pressure resistance of DI can and excellent necked-in property was examined. The steel plate properties capable of satisfying both the current level of pressure resistance and the excellent necked-in property of the DI can certainly conflict with the fact that high strength is required on the one hand and softness is required on the other hand. Although the requirements are true, the present inventors have examined what the pressure resistance strength of the DI can and the strength of the necked-in portion are in one body. Conventionally, as shown in the above-mentioned investigation result of the conventional plating base plate for a soft DI can, the pressure resistance strength of the DI can and the strength of the necked-in part are proportional to the strength of the base plate. The higher the price, the higher the price. Therefore, it has been considered that the weight reduction due to the strength increase of the steel sheet and the improvement of the necked-in property due to the softening of the steel sheet are not compatible with each other.

【００１９】本発明者等は、種々検討した結果、ＤＩ缶
の耐圧強度は、ＤＩ加工された後ＢＨ熱処理相当の焼き
付け塗装が施されたＤＩ缶のボトム部の鋼板の変形抵抗
で、その変形抵抗は、ボトム部のドーム加工が行われた
（数％の加工歪）後ＢＨ熱処理が施された部位の変形抵
抗である。一方、ネックドイン部の強度は、２回の絞り
成形後３回のアイアニング(ironing）加工が施された
｛合計の絞り比で約２．０の絞り歪と板厚歪で約４０％
（伸び率では約６７％に相当）｝後更にＢＨ熱処理が施
された加工歪の極めて高い部位の変形抵抗である。従っ
て、この両方の強度は、どちらも予変形後ＢＨ熱処理が
施された後の変形抵抗という点では同じであるが、両者
の予変形の歪量が大きく異なるという大きな差異があ
り、必ずしも同じものではなく、鋼の特性を充分に活用
すれば、その特性値は各々独立して変え得る可能性のあ
る因子であることに気づき、種々の実験を行い、本発明
の鋼を見いだしたものである。具体的には、数％の加工
後のＢＨ熱処理後の変形抵抗がより高く、且つ、板厚歪
で約４０％の加工後のＢＨ熱処理後の変形抵抗がより低
い鋼であればよいとの考えである。As a result of various studies by the present inventors, the compressive strength of the DI can is determined by the deformation resistance of the steel plate at the bottom of the DI can which has been DI-processed and then subjected to baking coating corresponding to BH heat treatment. The resistance is the deformation resistance of the portion where the dome processing of the bottom portion is performed (processing strain of several%) and then the BH heat treatment is performed. On the other hand, the strength of the necked-in part was subjected to ironing processing three times after drawing twice (drawing strain of about 2.0 at total drawing ratio and about 40% at plate thickness distortion).
(Corresponding to an elongation of about 67%)} BH heat treatment is further applied to the deformation resistance of a portion having an extremely high processing strain. Therefore, although both of these strengths are the same in terms of the deformation resistance after the pre-deformation BH heat treatment, there is a big difference in that the pre-deformation strain amounts are largely different, and they are not necessarily the same. However, if the properties of the steel are fully utilized, the property value is a factor that may possibly be changed independently, and various experiments were conducted to find the steel of the present invention. . Specifically, it is only necessary that the steel has a higher deformation resistance after BH heat treatment after working of several% and a lower deformation resistance after BH heat treatment after working of about 40% in plate thickness strain. It is an idea.

【００２０】先ず、本発明者等は、この考えに基づき、
ＤＩ缶の耐圧強度、ネックドイン性と従来のＴ−４ＣＡ
ならびに種々試作した鋼を用い、目標とする材質指標を
明らかにするための検討を行った。色々な鋼板を試作し
検討した結果、ＤＩ缶の耐圧強度とネックドイン部の強
度は、鋼板のＹ．Ｐ（３％ＢＨ）とＹ．Ｐ（５０％Ｂ
Ｈ）とで代表し得ること、を見いだした。尚、ＤＩ缶の
ネックドイン部の強度は、板厚歪で約４０％（伸び率で
は６７％）もの極めて高い歪を与えた後の変形抵抗を本
来評価するのが好ましいが、１）種々の鋼板について調
査した結果、伸び率で５０％の時の変形抵抗でもって、
板厚歪４０％の変形抵抗の測定値の代用が充分に可能な
こと、２）板厚歪で４０％もの高い歪が付与された後の
変形抵抗（ＪＩＳ−＃５試験片による降伏応力）の測定
は、引張り試験片の加工精度等の影響を受け易く測定値
にバラツキが生じることからネックドイン部の強度は、
鋼板のＹ．Ｐ（５０％ＢＨ）でもって指標値とした。First of all, the present inventors, based on this idea,
Pressure resistance strength of DI can, necked-in property and conventional T-4CA
Also, using various trial-produced steels, studies were conducted to clarify the target material index. As a result of prototyping various steel plates and examining them, the pressure resistance strength of the DI can and the strength of the necked-in part were found to be Y. P (3% BH) and Y. P (50% B
H) and what can be represented. The strength of the necked-in portion of the DI can is preferably originally evaluated for the deformation resistance after being subjected to an extremely high strain of about 40% in plate thickness strain (67% in elongation), but 1) various steel plates As a result of the investigation, the deformation resistance when the elongation rate is 50%,
Sufficient substitution of the measured value of deformation resistance of 40% of plate thickness strain is possible. 2) Deformation resistance after a strain as high as 40% of plate thickness strain is applied (yield stress by JIS- # 5 test piece). The measurement of is easily affected by the processing accuracy of the tensile test piece, etc.
Y. The index value was defined as P (50% BH).

【００２１】次に、ＤＩ缶の現状レベルの耐圧強度と優
れたネックドイン性を両立させる条件について検討し
た。図１は、これまで軽量化のために使用されてきたＤ
Ｉ缶用のＴ−４ＣＡ、以前に使用されていた箱焼鈍（Ｂ
ＡＦ）のＡｌ−Ｋ鋼をベースにＰ，Ｍｎを添加すること
によって原板のＹ．Ｐを高くした鋼板、極低炭素Ａｌ−
Ｋ鋼をベースにＣ含有量と焼鈍条件を変え鋼板中の固溶
Ｃを増加させることによって原板のＹ．Ｐを高くした鋼
板とＮｂ添加極低炭素鋼をベースに高い調質圧延率（以
下ＨＲＴと記す）によって原板のＹ．Ｐを高くした鋼板
について、原板のＹ．ＰとＹ．Ｐ（３％ＢＨ）及びＹ．
Ｐ（５０％ＢＨ）との関係を示した図である。図１か
ら、耐圧力は、Ｙ．Ｐ（３％ＢＨ）が３４kgf/mm² 以上
３９kgf/mm² 未満で良好な値が得られ、ネックドイン時
のしわ発生についてはＹ．Ｐ（５０％ＢＨ）が６２kgf/
mm² 以下、好ましくは６０kgf/mm² で良好となることが
わかり、本発明が優れていることがよくわかる。Next, the conditions under which the current level of pressure resistance of the DI can and the excellent necked-in property are compatible were examined. Fig. 1 shows the D that has been used to reduce the weight.
T-4CA for I cans, previously used box annealing (B
AF) Al-K steel as a base, and by adding P and Mn, Y. Steel plate with high P, ultra-low carbon Al-
Based on the K steel, the C content and annealing conditions were changed to increase the solute C in the steel sheet, thereby increasing the Y. Based on a steel sheet with a high P and an Nb-added ultra-low carbon steel, a high temper rolling ratio (hereinafter referred to as HRT) was used to improve the Y. For steel plates with a high P, Y. P and Y. P (3% BH) and Y.
It is a figure showing the relation with P (50% BH). From FIG. 1, the withstand pressure is Y. P (3% BH) of 34 kgf / mm ² or more and less than 39 kgf / mm ² gave good values. P (50% BH) is 62 kgf /
mm ² or less, preferably found to be a good in 60 kgf / mm ^2, well understood that the present invention is superior.

【００２２】更に、図１の結果から、注目すべき点は２
点あることもわかる。１点目は、ネックドイン性につい
てであり、ネックドイン性は、原板のＹ．Ｐが高くても
良好なものがある一方、原板のＹ．Ｐが低くても劣悪な
ネックドイン性のものもある点である。即ち、本発明者
等の調査によって、ネックドイン性は原板のＹ．Ｐから
は判断できず、本発明の評価方法のＹ．Ｐ（５０％Ｂ
Ｈ）の値で判断できることを初めて明らかにすることが
できた点である。２点目は、例えば、図１に示すよう
に、ＢＡＦ−Ａｌ−Ｋ鋼にＰ，Ｍｎを添加して単に原板
のＹ．Ｐを上昇させた鋼板は、現状レベルの耐圧強度と
優れたネックドイン性とが両立する範囲はないが、極低
炭素Ａｌ−Ｋ鋼をベースにＣ含有量と焼鈍条件を変え、
鋼板中の固溶Ｃを増加させることによって原板のＹ．Ｐ
を高くした鋼板や、Ｎｂ添加極低炭素鋼をベースにＨＲ
Ｔによって原板のＹ．Ｐを高くした鋼板は、ある条件下
では両立する範囲があることが明らかになった点であ
る。Further, from the result shown in FIG.
You can see that there are points. The first point is the necked-in property, and the necked-in property is Y. Even if the P is high, there are some good ones, while the Y. The point is that even if P is low, some have poor necked-in properties. That is, according to the investigation by the present inventors, the necked-in property is Y. It is not possible to judge from P.P. P (50% B
This is the first point that I was able to clarify what can be judged by the value of H). The second point is, for example, as shown in FIG. 1, by adding P and Mn to the BAF-Al-K steel, the Y. The steel sheet with increased P does not have a range where the pressure resistance at the current level and the excellent necked-in property are compatible, but the C content and the annealing conditions are changed based on the ultra-low carbon Al-K steel,
By increasing the solid solution C in the steel sheet, the Y. P
HR based on high steel plate and ultra low carbon steel with Nb added
The original plate Y. It is clear that the steel sheet with a higher P has a compatible range under certain conditions.

【００２３】以上、図１ならびに上記で説明したよう
に、本発明の鋼板の主なポイントの「Ｙ．Ｐ（３％Ｂ
Ｈ）が３４kgf/mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５
０％ＢＨ）が６２kgf/mm² 以下、好ましくは６０kgf/mm
² 以下であることを特徴とするＤＩ缶用表面処理原板」
は、ボトム部の現状レベルの耐圧強度の確保と優れたネ
ックドイン性を有することとの両立が可能となる優れた
ＤＩ缶用メッキ原板であり、工業的価値が極めて高いこ
とがわかる。As described above with reference to FIG. 1 and the above, the main points of the steel sheet of the present invention, “YP (3% B
H) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P (5
0% BH) is 62 kgf / mm ² or less, preferably 60 kgf / mm
Surface-treated original plate for DI can characterized by being ² or less "
Is an excellent plating base plate for a DI can that can achieve both the current level pressure resistance strength of the bottom part and the excellent necked-in property, and it can be seen that it has an extremely high industrial value.

【００２４】次に、本発明の請求項(3) は、図１のＮｂ
添加極低炭素鋼をベースにＨＲＴによって原板のＹ．Ｐ
を高くした鋼板は、どんな条件でも両立するわけではな
いが、ある条件下では両立する範囲があることに着目
し、更に、その最適条件を検討し、「鋼板中の固溶Ｃ量
を５ppm 未満とした後、調質圧延で伸び率で５％以上１
５％以下の歪を付与し、鋼板のＹ．Ｐ（３％ＢＨ）を３
４kgf/mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５０％Ｂ
Ｈ）を６２kgf/mm² 以下に調整することを特徴とするネ
ックドイン性に優れたＤＩ缶用表面原板の製造方法」の
方法を見いだしたものである。Next, claim (3) of the present invention relates to Nb of FIG.
Based on the added ultra-low carbon steel, the Y. P
A steel sheet with a high temperature does not meet all conditions, but it is noted that there is a range where it is compatible under certain conditions. Furthermore, the optimum conditions are examined, and "a solid solution C content in the steel sheet is less than 5 ppm. After tempering, 5% or more in elongation by temper rolling 1
A strain of 5% or less is applied, and the Y. P (3% BH) 3
4 kgf / mm ² or more 39kgf / mm less than ^2, Y. P (50% B
H) is adjusted to 62 kgf / mm ² or less, and a method for producing a surface original plate for DI can excellent in necked-in property ”is found.

【００２５】本発明の請求項(4) は、図１の極低炭素Ａ
ｌ−Ｋ鋼をベースにＣ含有量と焼鈍条件を変え鋼板中の
固溶Ｃを増加させることによって原板のＹ．Ｐを高くし
た鋼板の結果に着目し、更に、その最適条件を検討し、
「鋼板中の固溶Ｃ量を５ppm〜４０ppm 残留せしめ、そ
の後、調質圧延でドライ調質圧延が可能な伸び率で７％
未満好ましくは２％以上の歪を付与し、鋼板のＹ．Ｐ
（３％ＢＨ）を３４kgf/mm² 以上３９kgf/mm² 未満、
Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm² 以下に調整するこ
とを特徴とするネックドイン性に優れたＤＩ缶用表面処
理原板の製造方法」の方法を見いだしたものである。Claim (4) of the present invention relates to the extremely low carbon A of FIG.
Based on the I-K steel, the C. content and annealing conditions were changed to increase the solute C in the steel sheet, thereby increasing the Y.V. Paying attention to the result of the steel plate with higher P, and further examining the optimum conditions,
"The amount of solid solution C in the steel sheet is allowed to remain in the range of 5 to 40 ppm, and then the elongation rate at which the dry temper rolling can be performed in the temper rolling is 7%.
Less than 2%, preferably 2% or more of strain is applied, and the Y. P
(3% BH) to 34kgf / mm ² or more 39kgf / mm less than ^2,
Y. The method for producing a surface-treated original plate for a DI can having an excellent necked-in property is characterized by adjusting P (50% BH) to 62 kgf / mm ² or less.

【００２６】尚、ＤＩ缶の中には、特に厳しいフランジ
加工が行われる用途もあり、そのような用途に適用する
には、より優れたフランジ加工性が要求される。そこ
で、本発明者等は、このような厳しいフランジ加工に耐
え得る鋼板特性についても検討した。先ず、本発明を達
成するメタラジー手段である「Ｃ：０．０００５〜０．
００６０のＡｌ−Ｋ鋼を用い、焼鈍後最高１５％の調質
圧延により、多くの歪を与える方法」の本発明の請求項
(3) とは目的も利用分野も共に異なると鋼板の製造法で
あるが、「単なるストレッチャストレインの発生しない
鋼板の製造法として開示されている特公昭６３−３０３
６８号公報や特公平１−５２４５１号公報」に記載され
ている鋼板の製造条件（同公報の実施例の製造条件）を
参考に、成分、焼鈍、調質圧延率を変化させ、本発明鋼
板の特性値になるように種々調整し検討し、フランジ加
工性を調査した。しかし、フランジ加工性が不足するも
のもあるという結果になった。そこで、その原因を調査
するため鋼板の特性値とフランジ加工性の関係について
種々検討した結果、焼鈍板の結晶粒径とフランジ加工性
との間に顕著な相関があり、結晶粒径が小さいほどフラ
ンジ加工性が改善されるが、上記の同公報の実施例の製
造法に準じた上記の試験材ではＧ．Ｓｎｏが７〜８．５
程度で、最も細粒なものでも８．５板程度で充分なフラ
ンジ加工性を得るには結晶粒径が大きすぎ、更に改善す
る必要があることが明らかになった。There are some uses in which the DI can is subjected to particularly severe flanging, and a higher flanging property is required for application to such uses. Therefore, the present inventors have also examined the steel plate characteristics that can withstand such severe flanging. First, “C: 0.0005 to 0.
The invention of "a method of giving a large amount of strain by temper rolling up to 15% after annealing using Al-K steel No. 0060"
Although (3) is a method for producing a steel sheet that has different purposes and fields of use, it is "a method disclosed in Japanese Patent Publication No. 63-303 disclosed as a method for producing a steel sheet that does not generate mere stretcher strain.
No. 68 and Japanese Patent Publication No. 1-52451 ”, the steel sheet of the present invention is manufactured by changing the composition, annealing, and temper rolling rate with reference to the steel sheet production conditions (production conditions of Examples of the publication). Various adjustments were made so as to obtain the characteristic values of, and the flange formability was investigated. However, the result is that some of them lack flange workability. Therefore, in order to investigate the cause, as a result of various studies on the relationship between the characteristic value of the steel sheet and the flange formability, there is a significant correlation between the crystal grain size of the annealed sheet and the flange formability, and the smaller the crystal grain size is. Although the flange machinability is improved, in the above test material according to the manufacturing method of the example of the above-mentioned publication, G. Sno is 7-8.5
However, even with the finest grain, the crystal grain size was too large to obtain sufficient flanging workability with about 8.5 plates, and it became clear that further improvement is necessary.

【００２７】本発明者等は、焼鈍板の結晶粒径を細粒化
する方法について検討した結果、熱延時の仕上げ温度が
大きな影響を及ぼしており、仕上げ温度を８９０℃以上
好ましくは９００℃とすることで、熱延板の結晶粒が顕
著に細粒化しＧ．Ｓｎｏが９．０以上になり、充分なフ
ランジ加工性も確保できることがわかった。また、Ｇ．
Ｓｎｏが９．５以上になると、更に優れたフランジ加工
性が確保できることもわかり、請求項(2) のフランジ加
工性も優れた表面処理原板並びに請求項(5) の方法を見
いだすことができた。The inventors of the present invention have studied the method of reducing the crystal grain size of the annealed sheet, and as a result, the finishing temperature during hot rolling has a great influence, and the finishing temperature is 890 ° C. or higher, preferably 900 ° C. By doing so, the crystal grains of the hot-rolled sheet are remarkably fine-grained and G. It was found that Sno was 9.0 or more, and sufficient flange formability could be secured. In addition, G.
It was also found that when Sno is 9.5 or more, further excellent flange formability can be secured, and the surface-treated original plate having excellent flange formability of claim (2) and the method of claim (5) could be found. .

【００２８】また、本発明の請求項(4) の「鋼板中の固
溶Ｃ量を５ppm 〜４０ppm 残留せしめる方法」につい
て、製鋼での鋼の製造が容易なＣ含有量が高い領域につ
いても検討し、請求項(6) の「Ｃ：０．０１００〜０．
０７００％のＡｌ−Ｋ鋼を用い、連続焼鈍法で再結晶温
度〜８３０℃で再結晶焼鈍を行い、その後、３００〜５
５０℃で２０sec 以上の過時効処理を行い、室温まで冷
却し、鋼板中の固溶Ｃ量を５ppm 〜２０ppm と低減し、
その後、調質圧延で伸び率で２％以上１５％以下の歪を
付与し、鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上
３９kgf/mm² 未満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm
² 以下に調整することを特徴とするネックドイン性に優
れたＤＩ缶用表面処理原板の製造方法」を見いだした。Further, with respect to the "method for allowing the amount of solid solution C in the steel sheet to remain in the range of 5 ppm to 40 ppm" according to claim (4) of the present invention, the region where the C content is high in which the steel can be easily manufactured is also examined. Then, “C: 0.0100 to 0.
Using 0700% Al-K steel, recrystallization annealing was performed by a continuous annealing method at a recrystallization temperature of 830 ° C., and then 300 to 5
Perform overaging treatment for 20 seconds or more at 50 ° C, cool to room temperature, and reduce the amount of dissolved C in the steel sheet to 5ppm to 20ppm.
Then, a strain of 2% or more and 15% or less in elongation rate is applied by temper rolling, and the Y. P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P (50% BH) is 62 kgf / mm
^The method for producing a surface-treated original plate for a DI can excellent in necked-in property characterized by adjusting to ² or less was found.

【００２９】請求項(7) は、請求項(3) の「鋼板中の固
溶Ｃ量を５ppm 未満とした後、調質圧延で５％以上１５
％以下の歪に付与し、鋼板のＹ．Ｐ（３％ＢＨ）を３４
kgf/mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５０ＢＨ）を
６２kgf/mm² 以下に調整法する方法」について、この考
えを鋼板中の固溶Ｃ量が５ppm 未満となる箱焼鈍に適用
する方法を検討し、「Ｃ：０．０００５〜０．０７００
％のＡｌ−Ｋ鋼を、箱焼鈍法で再結晶温度〜７５０℃で
再結晶焼鈍を行い、室温まで空冷し、その後、調質圧延
で伸び率を５％以上１５％以下の歪を付与し、鋼板の
Ｙ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上３９kgf/mm² 未
満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm²以下に調整す
ることを特徴とするネックドイン性に優れたＤＩ缶用表
面処理原板の製造方法を見いだしたものである。Claim (7) is 5% or more and 15% by temper rolling after the amount of solute C in the steel sheet is less than 5 ppm in claim (3).
% Of the strain, the Y. P (3% BH) 34
kgf / mm ² or more 39kgf / mm less than ^2, Y. "Method of adjusting P (50BH) to 62 kgf / mm ² or less", a method of applying this idea to box annealing in which the amount of dissolved C in the steel sheet is less than 5 ppm was examined, and "C: 0.0005- 0.0700
% Al-K steel is recrystallized by the box annealing method at a recrystallization temperature of 750 ° C., air-cooled to room temperature, and then temper-rolled to impart an elongation of 5% or more and 15% or less. , Y. P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. The inventors have found a method for producing a surface-treated original plate for a DI can having excellent necked-in properties, which is characterized by adjusting P (50% BH) to 62 kgf / mm ² or less.

【００３０】更に、本発明者等は、結晶粒径が大きくな
り易い極低炭素鋼において、Ｇ．Ｓｎｏを９．０以上に
する請求項(5) とは別の方法についても検討し、請求項
(3)の連続焼鈍時に、少なくとも５００℃以上の温度域
を１００〜２５００℃／ｓで加熱し、再結晶温度〜９２
０℃で５秒以下の保定を行う再結晶焼鈍をする方法を見
いだした。この方法では、熱延の仕上げ温度によらず、
鋼板のＧ．Ｓｎｏを９以上に、更に、９．５以上とする
ことが可能となり、フランジ加工性をも確保できること
もわかった。Furthermore, the inventors of the present invention have found that G. A method different from the claim (5) in which Sno is set to 9.0 or more is also examined, and the claim
At the time of continuous annealing of (3), at least a temperature range of 500 ° C. or higher is heated at 100 to 2500 ° C./s to obtain a recrystallization temperature of −92.
We have found a method of performing recrystallization annealing that holds at 0 ° C. for 5 seconds or less. In this method, regardless of the finishing temperature of hot rolling,
G. of steel plate It was also found that Sno can be set to 9 or more, and further to 9.5 or more, and flange formability can be secured.

【００３１】以下に鋼板の構成条件について詳細に述べ
る。Ｃは、各請求項の製造条件によって上限の値は個別
に規制する必要がある。請求項(1), (2)では、０．０７
００％超になると、どのような製造条件の原板でも、鋼
板中のセメンタイト量が多くなりすぎフランジ加工性や
ネックドイン性が確保できなくなるので、上限値を０．
０７００％とした。請求項(3), (5), (8) では、０．０
０６０％超になると、焼鈍後の鋼板中の固溶Ｃ量を５pp
m 以下にすることが困難となるので、上限値を０．００
６０％とした。請求項(4) では、０．００６０％超にな
ると、鋼板中の固溶Ｃ量を４０ppm 以下にすることがで
きなくなるので、上限値を０．００６０％とした。請求
項(6) では、０．０１００％未満になると、過時効処理
中の固溶Ｃの減少速度が顕著に低下し、鋼板中の固溶Ｃ
量を４０ppm 以下にすることが困難になるので、下限値
を０．０１００％とした。請求項(8) は、請求項(1) と
同じ理由で上限値を０．０７００％とした。尚、下限値
の０．０００５％以上は、通常の製造法では０．０００
５％未満のものは造れないので、下限値を０．０００５
％とした。The constituent conditions of the steel sheet will be described in detail below. Regarding C, the upper limit value must be individually regulated according to the manufacturing conditions of each claim. In claims (1) and (2), 0.07
If it exceeds 00%, the amount of cementite in the steel sheet will be too large for any original plate under any manufacturing conditions, and the flange formability and necked-in property cannot be ensured.
It was set to 0700%. In claims (3), (5) and (8), 0.0
If it exceeds 060%, the amount of solute C in the steel sheet after annealing is 5 pp.
Since it is difficult to make m or less, the upper limit is 0.00
It was set to 60%. In claim (4), if it exceeds 0.0060%, the amount of solute C in the steel sheet cannot be made 40 ppm or less, so the upper limit was made 0.0060%. According to claim (6), when it is less than 0.0100%, the rate of decrease of the solid solution C during overaging treatment is significantly reduced, and the solid solution C in the steel sheet is reduced.
Since it becomes difficult to reduce the amount to 40 ppm or less, the lower limit value was made 0.0100%. The upper limit of claim (8) is set to 0.0700% for the same reason as claim (1). In addition, 0.0005% or more of the lower limit is 0.000 in the usual manufacturing method.
We cannot make less than 5%, so the lower limit is 0.0005.
%.

【００３２】Ｓｉ，Ｍｎ，Ｐ，Ｓは、何れも、鋼板の耐
食性に大きく影響を及ぼす元素で、耐食性の観点から、
それぞれ、≦０．３０％、≦１．００％、≦０．３０
％、≦０．２５％とする必要がある。尚、Ｍｎは、熱延
時の耳荒れ性の観点から、少なくとも０．０５％以上含
有する必要があるので、下限値を０．０５％とした。他
のＳｉ，Ｐ，Ｓは少なくても障害となることがないので
下限値を規制しなかった。Si, Mn, P, and S are all elements that greatly affect the corrosion resistance of the steel sheet. From the viewpoint of corrosion resistance,
≤0.30%, ≤1.00%, ≤0.30, respectively
%, ≤0.25%. In addition, since Mn needs to be contained at least 0.05% or more from the viewpoint of ear roughness during hot rolling, the lower limit was made 0.05%. The other Si, P, and S did not hinder at least, so the lower limit value was not regulated.

【００３３】sol.Ａｌは、脱酸剤として用いられ、０．
００２％は残留するので下限値を０．００２％とした。
また、０．１００％超になると鋳造時に溶鋼の空気酸化
が起こり易くなり介在物量が増え、加工性や、めっき品
質をも劣化させるようになるので０．１００％を上限値
とした。Sol.Al is used as a deoxidizing agent, and
002% remains, so the lower limit was made 0.002%.
Further, if it exceeds 0.100%, air oxidation of the molten steel is likely to occur during casting, the amount of inclusions increases, and the workability and plating quality also deteriorate, so 0.100% was made the upper limit value.

【００３４】Ｎは、０．０１００％超含有すると結晶粒
の細粒化が顕著になりプレス加工性が劣化するので上限
値を０．０１００％とした。尚、Ｎはいくら少なくなっ
ても、材質に悪影響を及ぼすことがないので特に規制す
る必要がない。If the content of N exceeds 0.0100%, the grain size of the crystal grains becomes remarkable and the press workability deteriorates, so the upper limit was made 0.0100%. It should be noted that no matter how small the amount of N is, it does not have a bad influence on the material, so there is no need to regulate it.

【００３５】Ｂは、ＮをＢＮとして固定し鋼板を軟質化
したいときには適宜添加すればよい。Ｂ含有量が０．０
０１０＋１．８×Ｎ％超になるとＢの固溶強化による硬
質化が顕著になるので、上限値を０．００１０＋１．８
×Ｎ％とした。B may be appropriately added when N is fixed as BN and the steel sheet is softened. B content is 0.0
If the content exceeds 010 + 1.8 × N%, the solidification of B will cause remarkable hardening, so the upper limit is 0.0010 + 1.8.
× N%.

【００３６】ＮｂやＴｉは、より高いｒ値や焼鈍板の結
晶粒径を細粒にしたり、図１にも示されているようによ
り低いＹ．Ｐ（５０％ＢＨ）を得、更にネックドイン性
を向上させたい場合に添加すれば良いが、Ｎｂ及びＴｉ
の１種または２種が０．０５０％超になっても合金コス
トが高くなるばかりで、材質の向上効果が飽和してしま
うようになるので、上限値を０．０５０％とした。請求
項(3) の場合は、Ｎｂ及びＴｉの１種または２種が０．
０３０％超になると、連続焼鈍時の再結晶温度が８３０
℃を超えるようになるので上限値を０．０３０％とし
た。請求項(4) の場合は、Ｎｂ及びＴｉの１種または２
種が０．０１０％を超えると、必要な固溶Ｃ量を５ppm
以上に残留せしめることができなくなるので、上限値を
０．０１０％とした。Nb and Ti have a higher r value, a finer grain size in the annealed plate, and a lower Y.V. as shown in FIG. P (50% BH) can be obtained and added when it is desired to further improve the necked-in property. Nb and Ti
Even if one or two of the above exceeds 0.050%, the alloy cost will not only increase, but the effect of improving the material will be saturated, so the upper limit was made 0.050%. In the case of claim (3), one or two kinds of Nb and Ti are 0.
If it exceeds 030%, the recrystallization temperature during continuous annealing is 830.
Since the temperature will exceed 0 ° C, the upper limit was made 0.030%. In the case of claim (4), one or two of Nb and Ti
If the seed exceeds 0.010%, the required amount of solid solution C is 5ppm
Since it becomes impossible to make it remain above, the upper limit was made 0.010%.

【００３７】請求項(7) の場合も、Ｎｂ及びＴｉの１種
または２種が０．０５０％超になっても合金コストが高
くなるばかりで、材質の向上効果が飽和してしまうよう
になるので、上限値を０．０５０％とした。現状レベル
の耐圧強度と優れたネックドイン性を両立させるには、
前述のように、「鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/
mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５０％ＢＨ）を６
２kgf/mm² 以下」であることが不可欠であるので、鋼板
のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上、Ｙ．Ｐ（５
０％ＢＨ）を６２kgf/mm² 以下に規制した。Ｙ．Ｐ（５
０％ＢＨ）の好ましい範囲は６０kgf/mm² 以下である。Also in the case of claim (7), even if the content of one or two of Nb and Ti exceeds 0.050%, not only the alloy cost increases but also the effect of improving the material is saturated. Therefore, the upper limit is set to 0.050%. To achieve both the current level of pressure resistance and excellent necked-in properties,
As described above, “YP of steel sheet (3% BH) is 34 kgf /
mm ² or more and less than 39 kgf / mm ² , Y. P (50% BH) 6
2 kgf / mm ² or less ”is essential. P (3% BH) is 34 kgf / mm ² or more, Y. P (5
0% BH) was regulated to 62 kgf / mm ² or less. Y. P (5
The preferable range of 0% BH) is 60 kgf / mm ² or less.

【００３８】固溶Ｃ量は、本発明の重要なポイントの１
つで、請求項(4) の方法では、図１に示すようにＹ．Ｐ
（５０％ＢＨ）を６２kgf/mm² 以下で、且つ、現状レベ
ルの耐圧強度を確保するのに必要な３４kgf/mm² のＹ．
Ｐ（３％ＢＨ）の確保は、固溶Ｃ量の適正化も重要であ
り、５ppm 未満では、ドライ調質圧延が可能な７％未満
の調質圧延率では困難となるので、下限値を５ppm とし
た。また、固溶Ｃ量が４０ppm 超になると、優れたネッ
クドイン性の確保が難しくなるので上限値を４０ppm と
した。請求項(6) の方法では、固溶Ｃ量が２０ppm 超に
なると、調質圧延率を調整しても、現状レベルの耐圧強
度と優れたネックドイン性との両立が難しくなるので、
上限値を２０ppm とした。尚、請求項(3) の方法で、鋼
板中の固溶Ｃ量の上限値を５ppm 未満としたのは、鋼板
中の固溶Ｃ量が５ppm 超のものには、経済的に有利なド
ライ調質圧延が可能な７％以下の調質圧延を行う請求項
(4) の方法を適用するのが経済的に有利になるので、請
求の範囲に入れなかった。The amount of dissolved C is one of the important points of the present invention.
Then, according to the method of claim (4), as shown in FIG. P
(50% BH) is 62 kgf / mm ² or less, and 34 kgf / mm ² of Y.
In order to secure P (3% BH), it is important to optimize the amount of solid solution C, and if it is less than 5 ppm, it will be difficult at a temper rolling rate of less than 7% that dry temper rolling is possible. It was set to 5 ppm. Further, if the amount of dissolved C exceeds 40 ppm, it becomes difficult to secure excellent necked-in property, so the upper limit was set to 40 ppm. In the method of claim (6), if the amount of solute C exceeds 20 ppm, it is difficult to achieve both the pressure resistance at the current level and the excellent necked-in property even if the temper rolling ratio is adjusted.
The upper limit was 20 ppm. In the method of claim (3), the upper limit of the amount of solid solution C in the steel sheet is set to less than 5 ppm because the amount of solid solution C in the steel sheet exceeds 5 ppm. A temper rolling of 7% or less, which enables temper rolling, is performed.
Since it is economically advantageous to apply the method of (4), it was not included in the scope of the claims.

【００３９】以下、鋼板の成分構成条件以外の製造条件
について詳細に述べる。鋳片の製造条件は、各請求項の
鋼の成分が得られる方法であればどのような方法でもよ
く、特に規制する必要はない。熱延条件も、特に規制す
る必要がなく、通常の熱延条件でよく、また、省エネル
ギーのための連続鋳造で製造された熱片を直接熱間圧延
を行う方法でも、熱片を加熱炉に挿入した後熱間圧延を
する方法でもよい。また、巻き取り温度も特に規制する
必要がないが、軟質材を得ようとする場合は中高温巻き
取りを採用するのがよい。尚、より優れたフランジ加工
性を得る場合には、請求項(5) に規制するように、仕上
げ温度を８９０℃以上好ましくは９００℃以上がよい。The production conditions other than the component constitution conditions of the steel sheet will be described in detail below. The production conditions of the cast slab may be any method as long as the components of the steel of each claim are obtained, and it is not particularly limited. The hot rolling conditions also do not need to be particularly regulated, and may be ordinary hot rolling conditions.Also, the hot strip produced by continuous casting for energy saving may be directly hot-rolled. A method of hot rolling after inserting may be used. Further, the winding temperature does not need to be particularly limited, but when obtaining a soft material, it is preferable to adopt medium-high temperature winding. In order to obtain a better flange formability, the finishing temperature is 890 ° C or higher, preferably 900 ° C or higher, as defined in claim (5).

【００４０】冷間圧延率は、ＤＩ缶のイヤリングに大き
く影響するので、８５〜９５％とする必要がある。尚、
ゼロに近いイヤリング率を得るためには、鋼の成分、熱
延条件、焼鈍条件を考慮し、微調整をするのが好まし
い。The cold rolling rate has a great effect on the earrings of DI cans, so it must be 85 to 95%. still,
In order to obtain an earring rate close to zero, it is preferable to make fine adjustments in consideration of steel composition, hot rolling conditions, and annealing conditions.

【００４１】再結晶焼鈍条件は、焼鈍方式によって大き
く異なるが、請求項(3) のような通常の連続焼鈍法では
再結晶温度〜８３０℃で再結晶焼鈍を行い、その後、室
温まで冷却すればよい。尚、焼鈍温度を８３０℃以下と
したのは、８３０℃超になると鋼板が軟化し通板中に延
びる等のトラブルが発生し焼鈍ができなくなるからであ
る。一方、請求項(8) の焼鈍の方法の、加熱速度で２桁
速く、焼鈍時間での約２桁短い従来の連続焼鈍炉とは全
く異なる機械設備のような焼鈍機ともよべる新しい焼鈍
設備では、焼鈍温度の上限は、通板性からの制限はな
く、材質上から決定すればよく、オーステナイトに入ら
ない温度まで許容できるので、上限値を９２０℃とし
た。また、焼鈍板の結晶粒径の細粒化効果を得るには、
少なくとも５００℃以上の温度域を１００℃／ｓ以上の
加熱速度で加熱することと、再結晶温度以上９２０℃以
下の温度域での滞在時間を１０sec 以下とする必要があ
る。尚、加熱速度の上限を２５００℃／ｓとしたのは、
それ以上の加熱速度では加熱速度が速すぎるため加熱終
点温度の制御が困難となるため、上限値を２５００℃／
ｓとした。The recrystallization annealing conditions vary greatly depending on the annealing method, but in the usual continuous annealing method as claimed in claim (3), recrystallization annealing is performed at a recrystallization temperature of 830 ° C. and then cooling to room temperature. Good. The annealing temperature is set to 830 ° C. or lower because if it exceeds 830 ° C., the steel sheet is softened and troubles such as extending into the threading occur and annealing cannot be performed. On the other hand, in the annealing method according to claim (8), the new annealing equipment called an annealing machine is completely different from the conventional continuous annealing furnace in which the heating speed is two orders of magnitude faster and the annealing time is about two orders of magnitude shorter. The upper limit of the annealing temperature is not limited by the sheet passing property and may be determined from the material, and the upper limit of the annealing temperature is set to 920 ° C. because it can be allowed to a temperature that does not enter austenite. Further, in order to obtain the effect of refining the crystal grain size of the annealed plate,
It is necessary to heat at least a temperature range of 500 ° C. or more at a heating rate of 100 ° C./s or more, and to make the residence time in the temperature range of the recrystallization temperature or more and 920 ° C. or less 10 seconds or less. The upper limit of the heating rate is 2500 ° C./s
If the heating rate is higher than that, it is difficult to control the heating end point temperature because the heating rate is too high.
s.

【００４２】請求項(6) の過時効処理を施す連続焼鈍法
では、焼鈍温度が再結晶温度以下ではＤＩ加工に耐え得
る延性が得られなくなり、８３０℃超では通板性が悪く
なるので、再結晶温度〜８３０℃で再結晶焼鈍を行う必
要がある。その後施される過時効処理は、３００〜５５
０℃で２０sec 以上の過時効処理条件を外れると、固溶
Ｃ量が５〜２０ppm とすることができなくなるので、過
時効処理条件を３００〜５５０℃で２０sec 以上に規制
した。In the continuous annealing method of performing the overaging treatment of claim (6), if the annealing temperature is lower than the recrystallization temperature, the ductility that can withstand DI processing cannot be obtained, and if it exceeds 830 ° C, the stripability deteriorates. It is necessary to perform recrystallization annealing at a recrystallization temperature of 830 ° C. The overaging treatment applied thereafter is 300 to 55.
If the condition of overaging for 20 seconds or longer at 0 ° C. is not satisfied, the amount of dissolved C cannot be set to 5 to 20 ppm, so the condition for overaging is regulated at 300 to 550 ° C. for 20 seconds or longer.

【００４３】調質圧延は、本発明の鋼板のポイントであ
る「鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上、３
９kgf/mm² 未満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm²
以下、好ましくは６０kgf/mm² 以下」にするために、固
溶Ｃ量の調整とともに、重要な要素である。請求項(3)
，(7) のように鋼板の固溶Ｃ量が５ppm 以下の場合
は、調質圧延率が５％未満では現状レベルの耐圧強度を
確保するための「鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/
mm² 以上３９kgf/mm² 未満」の確保ができなくなるの
で、下限値を５％とした。尚、上限値を１５％としたの
は本発明の鋼板が目的とする現状レベルの耐圧強度を維
持するには１５％で充分であること、また、より高い調
質圧延率を施すには経済的ロスが多くなるので上限値を
１５％とした。請求項(8) の上限値も同じ理由である。
請求項(4) の鋼板の固溶Ｃ量が５〜４０ppm と多い場合
には、下限値は通常の調質圧延率の１．０％程度でも
「鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上」の確
保ができるので、下限値を特に規制しなかったが、好ま
しくは、２％以上の調質圧延率を施すのがよく、より安
定して「鋼板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上
３９kgf/mm² 未満」の確保ができるようになる。尚、上
限値を７％未満としたのは経済的に有利なドライ調質圧
延が可能な調質圧延率が最高でも７％未満であるので上
限値を７％未満とした。請求項(6) の鋼板の固溶Ｃ量が
５〜２０ppm と多い場合には、２％未満の場合には「鋼
板のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上３９kgf/mm
² 未満」の確保ができなくなるので、下限値を２％とし
た。尚、上限値を１５％としたのは、上記の請求項(3)
と同じ理由である。The temper rolling is a key point of the steel sheet of the present invention, "YP of steel sheet (3% BH) is 34 kgf / mm ² or more, 3
Less than 9 kgf / mm ² , Y. P (50% BH) is 62 kgf / mm ²
Below, it is preferably 60 kgf / mm ² or less ", and is an important factor together with the adjustment of the amount of dissolved C. Claim (3)
, (7), when the amount of solute C in the steel sheet is 5 ppm or less, if the temper rolling rate is less than 5%, the "Y.P. (3% BH) 34 kgf /
mm ² or more and less than 39 kgf / mm ² ”cannot be secured, so the lower limit value was made 5%. It should be noted that the upper limit of 15% is sufficient for maintaining the desired level of pressure resistance of the steel sheet of the present invention at 15%, and it is economical to apply a higher temper rolling rate. The upper limit is set to 15% because the target loss increases. The upper limit of claim (8) is the same reason.
When the amount of solute C in the steel sheet according to claim (4) is as high as 5 to 40 ppm, the lower limit is "Y.P (3% BH) of steel sheet" even if it is about 1.0% of the ordinary temper rolling rate. 34 kgf / mm ² or more ”can be ensured, so the lower limit value is not particularly limited, but it is preferable to apply a temper rolling rate of 2% or more, and more stable“ Y. 3% BH) of 34 kgf / mm ² or more and less than 39 kgf / mm ² ”can be secured. The upper limit of less than 7% was set to less than 7% because the temper rolling rate at which economically advantageous dry temper rolling is possible is less than 7% at the maximum. When the amount of solid solution C of the steel sheet according to claim (6) is as large as 5 to 20 ppm, when it is less than 2%, “Y.P (3% BH) of the steel sheet is 34 kgf / mm ² or more 39 kgf / mm ² or more.
Since securing of less than ² "can not, and the lower limit and 2%. The upper limit of 15% is defined in the above claim (3).
For the same reason as.

【００４４】[0044]

【実施例】以下に本発明の効果を実施例により説明す
る。表１に成分、表２に連続熱延、冷間圧延、連続焼
鈍、調質圧延、条件で０．２４５mmの表面処理原板を製
造した。製造した表面処理原板の固溶Ｃ量、Ｙ．Ｐ（３
％ＢＨ）、Ｙ．Ｐ（５０％ＢＨ）を測定した。また、Ｓ
ｎメッキ後ＤＩ性能の調査を行った。その結果を表３に
示す。EXAMPLES The effects of the present invention will be described below with reference to examples. A 0.245 mm surface-treated original plate was produced under the conditions shown in Table 1 for components and Table 2 for continuous hot rolling, cold rolling, continuous annealing, temper rolling. The solid solution C content of the produced surface-treated original plate, Y. P (3
% BH), Y. P (50% BH) was measured. Also, S
The DI performance was investigated after n plating. The results are shown in Table 3.

【００４５】鋼Ａ，Ｂ，Ｃ，Ｄ，Ｅ，Ｆは、何れも本発
明の成分範囲内の鋼で、鋼Ａは、Ｃ量が０．００２５％
でＮｂを０．００６％添加した例、鋼Ｂは、Ｔｉを０．
０２５％添加した例、鋼Ｃは、Ｎｂを０．００７％、Ｂ
を０．０００８％添加した例、鋼Ｄは、Ｃが０．００１
１％と極めて低下させ、Ｎｂ，Ｔｉを添加しなくても焼
鈍後の固溶Ｃ量が５ppm 以下となる例、鋼Ｅは、Ｃ含有
量を０．００４５％と多くして焼鈍後の固溶Ｃ含有量を
３０ppm と増やした例、鋼Ｆは、Ｃ含有量を０．０４１
０％と通常の低炭素Ａｌ−Ｋ鋼のＣ含有量の例、であ
る。Steels A, B, C, D, E and F are all steels within the composition range of the present invention, and steel A has a C content of 0.0025%.
In the example in which 0.006% of Nb is added in steel B, steel B has a Ti content of 0.
An example in which 025% is added, Steel C contains 0.007% of Nb and B
Of 0.0008%, steel D has a C content of 0.001
An example in which the amount of solid solution C after annealing is 5 ppm or less without adding Nb and Ti, which is extremely decreased to 1%, steel E has a high C content of 0.0045% and has a solid content after annealing. In the case of increasing the content of molten C to 30 ppm, steel F has a C content of 0.041
It is an example of 0% and C content of usual low carbon Al-K steel.

【００４６】試料１，２，８，９，１０は、鋼１，２は
Ｃ量が０．００２５％でＮｂを０．００６％添加した
鋼、鋼８はＴｉを０．０２５％添加した鋼、鋼９はＮｂ
を０．００７％、Ｂを０．０００８％添加した鋼、鋼１
０は、Ｃが０．００１１％と極めて低下させ、Ｎｂ，Ｔ
ｉを添加しなくても焼鈍後の固溶Ｃ量が５ppm 以下とし
た鋼を用い、何れも本発明の請求項(2) 或いは(4) の実
施例で、何れも、本発明が目標とする材質指標のＹ．Ｐ
（３％ＢＨ）ならびにＹ．Ｐ（５０％ＢＨ）をクリヤ
し、現状レベルの耐圧強度を確保し、優れたネックドイ
ン性が得られた。また、別途、フランジ加工性を評価し
た結果、請求項(4) の実施例の試料２，８，９，１０は
何れも結晶粒が細粒で良好なフランジ加工性が得られ、
請求項(2) の鋼板はフランジ加工性にも優れることがわ
かる。Samples 1, 2, 8, 9 and 10 are steels 1 and 2 having a C content of 0.0025% and 0.006% of Nb, and steel 8 is a steel having 0.025% of Ti. , Steel 9 is Nb
With 0.007% of B and 0.0008% of B, Steel 1
0 significantly reduces C by 0.0011%, and Nb, T
Even if i is not added, a steel having a solid solution C content of 5 ppm or less after annealing is used, and both are examples of claim (2) or (4) of the present invention. The material index Y. P
(3% BH) and Y. By clearing P (50% BH), the current level of pressure resistance was secured and excellent necked-in property was obtained. In addition, as a result of separately evaluating the flange formability, in Samples 2, 8, 9, and 10 of the embodiment of claim (4), the crystal grains are fine and good flange formability is obtained.
It can be seen that the steel plate of claim (2) is also excellent in flange formability.

【００４７】試料３，４は、試料２と調質圧延率が３．
０％、１．０％と本発明の請求項(3) 及び(5) の調質圧
延率の範囲を外れた比較例で、何れも、本発明が目標と
する材質指標のＹ．Ｐ（３％ＢＨ）が２９．２６kgf/mm
² と低く外れ、現状レベルの耐圧強度が確保できなかっ
た。試料５は、Ｃ量が０．００２５％でＮｂを０．００
６％添加した鋼を用い、本発明の請求項(7) の箱焼鈍法
に適用した実施例で、本発明が目標とする材質指標の
Ｙ．Ｐ（３％ＢＨ）ならびにＹ．Ｐ（５０％ＢＨ）をク
リヤし、現状レベルの耐圧強度を確保し、優れたネック
ドイン性が得られている。Samples 3 and 4 have a temper rolling ratio of 3.
Comparative examples out of the range of the temper rolling ratios of 0% and 1.0% and claims (3) and (5) of the present invention. P (3% BH) is 29.26 kgf / mm
^It was as low as ² and the current level of pressure resistance could not be secured. Sample 5 had a C content of 0.0025% and a Nb content of 0.0025%.
In the example applied to the box annealing method according to claim (7) of the present invention using steel added with 6%, Y. P (3% BH) and Y. By clearing P (50% BH), the pressure resistance strength of the current level is secured, and excellent necked-in property is obtained.

【００４８】試料６は、試料５と調質圧延率が１．０％
と本発明の請求項(7) の調質圧延率の範囲を外れた比較
例で、本発明が目標とする材質指標のＹ．Ｐ（３％Ｂ
Ｈ）が２５kgf/mm² と低く外れ、現状レベルの耐圧強度
が確保できていない。試料７は、Ｃ量が０．００２５％
でＮｂを０．００６％添加した鋼を用い、本発明の請求
項(8) の超急速加熱短時間焼鈍法に適用した実施例で、
本発明が目標とする材質指標のＹ．Ｐ（３％ＢＨ）なら
びにＹ．Ｐ（５０％ＢＨ）をクリヤし、現状レベルの耐
圧強度を確保し、優れたネックドイン性が得られてい
る。また、フランジ加工性を評価した結果、Ｇ．Ｓｎｏ
が１０．５と顕著に細粒となっており優れたフランジ加
工性が得られ、請求項(2) の鋼板はフランジ加工性にも
優れることがわかる。Sample 6 has a temper rolling ratio of 1.0% as compared with Sample 5.
And a comparative example out of the range of the temper rolling ratio defined in claim (7) of the present invention, Y. P (3% B
H) is as low as 25 kgf / mm ^2, and the current level of pressure resistance cannot be secured. Sample 7 has a C content of 0.0025%
In an example applied to the ultra-rapid heating short-time annealing method of claim (8) of the present invention, using steel containing 0.006% of Nb added in
The material index Y. P (3% BH) and Y. By clearing P (50% BH), the pressure resistance strength of the current level is secured, and excellent necked-in property is obtained. In addition, as a result of evaluating the flange formability, G. Sno
It was found that the fine grain size was 10.5, and excellent flange formability was obtained, and the steel sheet of claim (2) was also excellent in flange formability.

【００４９】試料１１は、Ｃ含有量を０．００４５％と
多くして焼鈍後の固溶Ｃ含有量を３０ppm と増やした例
で、本発明の請求項(4) の経済的なドライ調質圧延法に
適用した実施例で、本発明が目標とする材質指標のＹ．
Ｐ（３％ＢＨ）ならびにＹ．Ｐ（５０％ＢＨ）をクリヤ
し、現状レベルの耐圧強度を確保し、優れたネックドイ
ン性が得られている。Sample 11 is an example in which the C content is increased to 0.0045% and the solid solution C content after annealing is increased to 30 ppm. The economical dry tempering according to claim (4) of the present invention. In the embodiment applied to the rolling method, Y.
P (3% BH) and Y. By clearing P (50% BH), the pressure resistance strength of the current level is secured, and excellent necked-in property is obtained.

【００５０】試料１２は、Ｃ含有量を０．０４１０％と
通常の低炭素Ａｌ−Ｋ鋼を用い、本発明の請求項(7) の
箱焼鈍法に適用した実施例で、本発明が目標とする材質
指標のＹ．Ｐ（３％ＢＨ）ならびにＹ．Ｐ（５０％Ｂ
Ｈ）をクリヤし、現状レベルの耐圧強度を確保し、優れ
たネックドイン性が得られている。Sample 12 is an example applied to the box annealing method of claim (7) of the present invention by using a normal low carbon Al-K steel having a C content of 0.0410%, and the present invention is aimed at. Of the material index Y. P (3% BH) and Y. P (50% B
H) is cleared, the pressure resistance strength of the present level is secured, and excellent necked-in property is obtained.

【００５１】試料１３は、試料１２と調質圧延率が１．
０％と本発明の請求項(7) の調質圧延率の範囲を外れた
比較例で、本発明が目標とする材質指標のＹ．Ｐ（３％
ＢＨ）が２６kgf/mm² と低く外れ、現状レベルの耐圧強
度が確保できていない。試料１４は、従来のＤＩ缶用の
Ｔ−４ＣＡの従来例で、本発明が目標とする材質指標の
Ｙ．Ｐ（５０％ＢＨ）が６６kgf/mm² と高く外れ、ネッ
クドイン時にしわが発生している。試料１５は、Ｃ含有
量を０．０４１０％と通常の低炭素Ａｌ−Ｋ鋼を用い、
本発明の請求項(6) の過時効処理を行う連続焼鈍法に適
用し、調質圧延率を２．５％とした実施例で、本発明が
目標とする材質指標のＹ．Ｐ（３％ＢＨ）ならびにＹ．
Ｒ（５０％ＢＨ）をクリヤし、現状レベルの耐圧強度を
確保し、優れたネックドイン性が得られている。Sample 13 has a temper rolling ratio of 1.
In the comparative example in which the temper rolling reduction ratio is outside the range of 0% and the temper rolling ratio of claim (7) of the present invention, Y. P (3%
BH) is as low as 26 kgf / mm ^2, and the current level of pressure resistance cannot be secured. Sample 14 is a conventional example of T-4CA for a conventional DI can, which has a material index of Y. P (50% BH) is as high as 66 kgf / mm ^{2, which} is off, and wrinkles occur during necked-in. Sample 15 used a normal low carbon Al-K steel with a C content of 0.0410%,
It is an example applied to the continuous annealing method for performing overaging treatment according to claim (6) of the present invention and the temper rolling rate is 2.5%. P (3% BH) and Y.
By clearing R (50% BH), the pressure resistance strength of the current level is secured, and excellent necked-in property is obtained.

【００５２】以上の実施例の結果から明らかなように、
本発明の鋼板の主なポイントの「Ｙ．Ｐ（３％ＢＨ）が
３４kgf/mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５０％Ｂ
Ｈ）が６２kgf/mm² 以下、好ましくは６０kgf/mm² 以下
であることを特徴とするＤＩ缶用表面処理原板」は、ボ
トム部の現状レベルの耐圧強度の確保と優れたネックド
イン性を有することとの両立が可能となる優れたＤＩ缶
加工性を有するＤＩ缶用メッキ原板で、工業的価値が極
めて高いこと、また、請求項(3) 〜(8) の製造方法によ
って製造できることがわかる。As is clear from the results of the above examples,
The main points of the steel sheet of the present invention are “Y.P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , YP (50% BH).
H) is 62kgf / mm ² or less, preferably DI can surface treatment master plate, characterized in that at most 60 kgf / mm ² "is to have a secure and good Nekkudoin of compressive strength of current level of the bottom portion It can be seen that it is a plated original plate for DI cans which has excellent processability for DI cans, and has an extremely high industrial value, and that it can be produced by the production method of claims (3) to (8).

【００５３】[0053]

【表１】 [Table 1]

【００５４】[0054]

【表２】 [Table 2]

【００５５】[0055]

【表３】 [Table 3]

【００５６】[0056]

【発明の効果】以上に本発明について詳細に説明した
が、本発明の鋼板は、現状レベルの耐圧強度とネックド
イン性に優れ、より厳しい成形のＤＩ缶に適用され優れ
た効果が発揮でき、通常の連続焼鈍設備の請求項(3),
(4), (5) の方法、過時効処理設備のある連続焼鈍法で
の請求項(6) 、箱焼鈍法での請求項(7) 、ならびに、極
めてコンパクトな連続焼鈍法での請求項(8) の方法で、
本発明の鋼板を製造することが可能となり、その工業的
価値は大である。The present invention has been described in detail above. However, the steel sheet of the present invention has excellent pressure resistance and necked-in properties at the current level, and can be applied to more severely molded DI cans to exert excellent effects. Claim of continuous annealing equipment of (3),
Claims (6) in the continuous annealing method with methods (4) and (5), overaging treatment equipment, claim (7) in the box annealing method, and claims in the extremely compact continuous annealing method By the method of (8),
It becomes possible to manufacture the steel sheet of the present invention, and its industrial value is great.

【図面の簡単な説明】[Brief description of drawings]

【図１】原板のＹ．ＰとＹ．Ｐ（３％ＢＨ）ならびに
Ｙ．Ｐ（５０％ＢＨ）との関係を示す図である。FIG. 1 shows Y. P and Y. P (3% BH) and Y. It is a figure which shows the relationship with P (50% BH).

───────────────────────────────────────────────────── フロントページの続き (72)発明者 井上 昭彦 兵庫県姫路市広畑区富士町１番地 新日本 製鐵株式会社広畑製鐵所内 (72)発明者 江連 和哉 兵庫県姫路市広畑区富士町１番地 新日本 製鐵株式会社広畑製鐵所内 (72)発明者 吉原 良一 兵庫県姫路市広畑区富士町１番地 新日本 製鐵株式会社広畑製鐵所内 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Akihiko Inoue 1 Fuji-machi, Hirohata-ku, Himeji-shi, Hyogo Nippon Steel Co., Ltd. Hirohata Works (72) Inventor Kazuya Eren 1 Fuji-cho, Hirohata-ku, Himeji-shi, Hyogo Address: Nippon Steel Co., Ltd., Hirohata Works (72) Inventor, Ryoichi Yoshihara, 1 Fuji-machi, Hirohata-ku, Himeji City, Hyogo Prefecture, Nippon Steel Works, Hirohata Works

Claims (8)

【特許請求の範囲】[Claims] 【請求項１】 重量％で、 Ｃ ：０．０００５〜０．０７００％、 Ｓｉ：≦０．３０％、 Ｍｎ：０．０５〜１．００％、 Ｐ ：≦０．０３０％、 Ｓ ：≦０．０２５％、 sol.Ａｌ：０．００２〜０．１００％、 Ｎ ：≦０．０１００％、 Ｂ ：０〜（０．００１０＋１．８×Ｎ％）％、 Ｎｂ及びＴｉの１種または２種：０〜０．０５０％、 残部不可避的不純物及び鉄よりなり、Ｙ．Ｐ（３％Ｂ
Ｈ）が３４kgf/mm² 以上３９kgf/mm² 未満、Ｙ．Ｐ（５
０％ＢＨ）が６２kgf/mm² 以下であることを特徴とする
ネックドイン性に優れたＤＩ缶用表面処理原板。1. By weight%, C: 0.0005 to 0.0700%, Si: ≤ 0.30%, Mn: 0.05 to 1.00%, P: ≤ 0.030%, S: ≤ 0.025%, sol.Al: 0.002 to 0.100%, N: ≦ 0.0100%, B: 0 to (0.0010 + 1.8 × N%)%, one or two of Nb and Ti. Species: 0-0.050%, balance unavoidable impurities and iron, Y. P (3% B
H) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P (5
0% BH) is 62 kgf / mm ² or less, which is a surface-treated original plate for DI can having excellent necked-in properties. 【請求項２】 請求項１の記載の表面処理原板におい
て、Ｇ．Ｓｎｏが９．０以上であることを特徴とするフ
ランジ加工性の良好なネックドイン性に優れたＤＩ缶用
表面処理原板。2. The surface-treated original plate according to claim 1, wherein A surface-treated original plate for a DI can which has a good flange formability and an excellent necked-in property, which has a Sno of 9.0 or more. 【請求項３】 重量％で、 Ｃ ：０．０００５〜０．００６０％、 Ｓｉ：≦０．３０％、 Ｍｎ：０．０５〜１．００％、 Ｐ ：≦０．０３０％、 Ｓ ：≦０．０２５％、 sol.Ａｌ：０．００２〜０．１００％、 Ｎ ：≦０．０１００％、 Ｂ ：０〜（０．００１０＋１．８×Ｎ％）％、 Ｎｂ及びＴｉの１種または２種：０〜０．０３％、 残部不可避的不純物及び鉄よりなる鋳片を、熱間圧延を
行い熱延鋼帯とし、８５〜９５％の冷間圧延率で冷間圧
延を行い、連続焼鈍法で再結晶温度〜８３０℃で再結晶
焼鈍を行い、室温まで冷却し、鋼板中の固溶Ｃ量を５pp
m 未満とした後、調質圧延で５％以上１５％以下の歪を
付与し、鋼板のＹ．Ｐ（３％ＢＨ）が３４kgf/mm² 以上
３９kgf/mm² 未満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm
² 以下に調整することを特徴とするネックドイン性に優
れたＤＩ缶用表面処理原板の製造方法。3. By weight%, C: 0.0005 to 0.0060%, Si: ≤ 0.30%, Mn: 0.05 to 1.00%, P: ≤ 0.030%, S: ≤ 0.025%, sol.Al: 0.002 to 0.100%, N: ≦ 0.0100%, B: 0 to (0.0010 + 1.8 × N%)%, one or two of Nb and Ti. Species: 0 to 0.03%, a slab composed of the balance unavoidable impurities and iron is hot rolled into a hot rolled steel strip, cold rolled at a cold rolling rate of 85 to 95%, and continuously annealed. Recrystallization annealing is carried out at a recrystallization temperature of ~ 830 ° C by the method, cooled to room temperature, and the amount of solid solution C in the steel sheet is 5 pp.
After being less than m, strain of 5% or more and 15% or less is applied by temper rolling, and the Y. P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P (50% BH) is 62 kgf / mm
^A method for producing a surface-treated original plate for a DI can excellent in necked-in property, which is adjusted to ² or less. 【請求項４】 重量％で、 Ｃ ：０．００２０〜０．００６０％、 Ｓｉ：≦０．３０％、 Ｍｎ：０．０５〜１．００％、 Ｐ ：≦０．０３０％、 Ｓ ：≦０．０２５％、 sol.Ａｌ：０．００２〜０．１００％、 Ｎ ：≦０．０１００％、 Ｂ ：０〜（０．００１０＋１．８×Ｎ％）％、 Ｎｂ及びＴｉの１種または２種：０〜０．０１％、 残部不可避的不純物及び鉄よりなる鋳片を、熱間圧延を
行い熱延鋼帯とし、８５〜９５％の冷間圧延率で冷間圧
延を行い、連続焼鈍法で再結晶温度〜８３０℃で再結晶
焼鈍を行い、室温まで冷却し、鋼板中の固溶Ｃ量を５pp
m 〜４０ppm 残留せしめ、その後、調質圧延でドライ調
質圧延が可能な伸び率で７％未満の歪を付与し、鋼板の
Ｙ．Ｐ（３％ＢＨ）が３４kgf/mm² 以上３９kgf/mm² 未
満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm² 以下に調整す
ることを特徴とするネックドイン性に優れたＤＩ缶用表
面処理原板の製造方法。4. By weight%, C: 0.0020 to 0.0060%, Si: ≤ 0.30%, Mn: 0.05 to 1.00%, P: ≤ 0.030%, S: ≤ 0.025%, sol.Al: 0.002 to 0.100%, N: ≦ 0.0100%, B: 0 to (0.0010 + 1.8 × N%)%, one or two of Nb and Ti. Species: 0 to 0.01%, a slab composed of the balance unavoidable impurities and iron is hot-rolled to form a hot-rolled steel strip, cold-rolled at a cold rolling rate of 85 to 95%, and continuously annealed. Recrystallization annealing is carried out at a recrystallization temperature of ~ 830 ° C by the method, cooled to room temperature, and the amount of solid solution C in the steel sheet is 5 pp.
m to 40 ppm is left, and after that, a strain of less than 7% is imparted at an elongation rate that enables dry temper rolling in temper rolling. P (3% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. A method for producing a surface-treated original plate for a DI can having excellent necked-in properties, which comprises adjusting P (50% BH) to 62 kgf / mm ² or less. 【請求項５】 請求項３の記載の方法において、熱間圧
延時に８９０℃以上好ましくは９００℃以上で仕上げ熱
延を行い熱延鋼帯とすることを特徴とするＧ．Ｓｎｏ：
９．０以上のフランジ加工性の良好なネックドイン性に
優れたＤＩ缶用表面処理原板の製造方法。5. The method according to claim 3, wherein hot rolling is performed by finish hot rolling at 890 ° C. or higher, preferably 900 ° C. or higher during hot rolling. Sno:
A method for producing a surface-treated original plate for a DI can having a flange workability of 9.0 or more and excellent necked-in properties. 【請求項６】 重量％で、 Ｃ ：０．０１００〜０．０７００％、 Ｓｉ：≦０．３０％、 Ｍｎ：０．０５〜１．００％、 Ｐ ：≦０．０３０％、 Ｓ ：≦０．０２５％、 sol.Ａｌ：０．００２〜０．１００％、 Ｎ ：≦０．０１００％、 Ｂ ：０〜（０．００１０＋１．８×Ｎ％）％、 残部不可避的不純物及び鉄よりなる鋳片を、熱間圧延を
行い熱延鋼帯とし、８５〜９５％の冷間圧延率で冷間圧
延を行い、連続焼鈍法で再結晶温度〜８３０℃で再結晶
焼鈍を行い、その後、３００〜５５０℃で２０sec 以上
の過時効処理を行い、室温まで冷却し、鋼板中の固溶Ｃ
量を５ppm 〜２０ppm と低減し、その後、調質圧延で伸
び率で２％以上１５％以下の歪を付与し、鋼板のＹ．Ｐ
（３％ＢＨ）を３４kgf/mm² 以上３９kgf/mm² 未満、
Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm²以下に調整するこ
とを特徴とするネックドイン性に優れたＤＩ缶用表面処
理原板の製造方法。6. By weight%, C: 0.0100 to 0.0700%, Si: ≤ 0.30%, Mn: 0.05 to 1.00%, P: ≤ 0.030%, S: ≤ 0.025%, sol.Al: 0.002 to 0.100%, N: ≦ 0.0100%, B: 0 to (0.0010 + 1.8 × N%)%, balance unavoidable impurities and iron The slab is hot-rolled into a hot-rolled steel strip, cold-rolled at a cold rolling rate of 85 to 95%, recrystallized at a recrystallization temperature of 830 ° C. by a continuous annealing method, and then, Perform overaging treatment at 300 to 550 ° C for 20 seconds or longer, cool to room temperature, and dissolve C in steel sheet.
The amount of the steel sheet is reduced to 5 ppm to 20 ppm and then strained by temper rolling to impart a strain of 2% or more and 15% or less. P
(3% BH) to 34kgf / mm ² or more 39kgf / mm less than ^2,
Y. A method for producing a surface-treated original plate for a DI can having excellent necked-in properties, which comprises adjusting P (50% BH) to 62 kgf / mm ² or less. 【請求項７】 重量％で、 Ｃ ：０．０００５〜０．０７００％、 Ｓｉ：≦０．３０％、 Ｍｎ：０．０５〜１．００％、 Ｐ ：≦０．０３０％、 Ｓ ：≦０．０２５％、 sol.Ａｌ：０．００２〜０．１００％、 Ｎ ：≦０．０１００％、 Ｂ ：０〜（０．００１０＋１．８×Ｎ％）％、 Ｎｂ及びＴｉの１種または２種：０〜０．０５０％、 残部不可避的不純物及び鉄よりなる鋳片を、熱間圧延を
行い熱延鋼帯とし、８５〜９５％の冷間圧延率で冷間圧
延を行い、箱焼鈍法で再結晶温度〜７５０℃で再結晶焼
鈍を行い、室温まで冷却し、その後、調質圧延で伸び率
で５％以上１５％以下の歪を付与し、鋼板のＹ．Ｐ（３
％ＢＨ）を３４kgf/mm² 以上３９kgf/mm²未満、Ｙ．Ｐ
（５０％ＢＨ）を６２kgf/mm² 以下に調整することを特
徴とするネックドイン性に優れたＤＩ缶用表面処理原板
の製造方法。7. By weight%, C: 0.0005 to 0.0700%, Si: ≤ 0.30%, Mn: 0.05 to 1.00%, P: ≤ 0.030%, S: ≤ 0.025%, sol.Al: 0.002 to 0.100%, N: ≦ 0.0100%, B: 0 to (0.0010 + 1.8 × N%)%, one or two of Nb and Ti. Species: 0-0.050%, a slab consisting of the balance unavoidable impurities and iron is hot-rolled to form a hot-rolled steel strip, cold-rolled at a cold-rolling rate of 85-95%, and annealed in a box. Recrystallization annealing is carried out at a recrystallization temperature of up to 750 ° C. by means of the C. method, then cooled to room temperature, and then temper-rolled to impart a strain of 5% or more and 15% or less to the Y. P (3
% BH) is 34 kgf / mm ² or more and less than 39 kgf / mm ² , Y. P
(50% BH) is adjusted to 62 kgf / mm ² or less, and a method for producing a surface-treated original plate for a DI can having excellent necked-in properties. 【請求項８】 重量％で、 Ｃ ：０．０００５〜０．００６０％、 Ｓｉ：≦０．３０％、 Ｍｎ：０．０５〜１．００％、 Ｐ ：≦０．０３０％、 Ｓ ：≦０．０２５％、 sol.Ａｌ：０．００２〜０．１００％、 Ｎ ：≦０．０１００％、 Ｂ ：０〜（０．００１０＋１．８×Ｎ％）％、 Ｎｂ及びＴｉの１種または２種：０〜０．０５０％、 残部不可避的不純物及び鉄よりなる鋳片を、熱間圧延を
行い熱延鋼帯とし、８５〜９５％の冷間圧延率で冷間圧
延を行い、その後再結晶焼鈍をするに際し、５００℃以
上の温度域を１００〜２５００℃／ｓの加熱速度で再結
晶温度〜９２０℃に加熱し、その温度域で０〜１０sec
滞在せしめて再結晶焼鈍を行い、室温まで冷却し、その
後、調質圧延で伸び率で１５％以下の歪を付与し、鋼板
のＹ．Ｐ（３％ＢＨ）を３４kgf/mm² 以上３９kgf/mm²
未満、Ｙ．Ｐ（５０％ＢＨ）を６２kgf/mm² 以下に調整
することを特徴とするＧ．Ｓｎｏ：９．０以上のフラン
ジ加工性の良好なネックドイン性に優れたＤＩ缶用表面
処理原板の製造方法。8. In% by weight, C: 0.0005 to 0.0060%, Si: ≤ 0.30%, Mn: 0.05 to 1.00%, P: ≤ 0.030%, S: ≤ 0.025%, sol.Al: 0.002 to 0.100%, N: ≦ 0.0100%, B: 0 to (0.0010 + 1.8 × N%)%, one or two of Nb and Ti. Species: 0 to 0.050%, a slab composed of the balance unavoidable impurities and iron is hot-rolled into a hot-rolled steel strip, cold-rolled at a cold rolling rate of 85-95%, and then re-rolled. When performing crystal annealing, a temperature range of 500 ° C or higher is heated to a recrystallization temperature of 920 ° C at a heating rate of 100 to 2500 ° C / s, and 0 to 10 seconds in the temperature range.
Recrystallization annealing is carried out by allowing it to stay, cooling to room temperature, and then temper rolling to impart a strain of 15% or less in elongation rate to the Y. P (3% BH) to 34kgf / mm ² or more 39kgf / mm ²
Less than Y. P. (50% BH) is adjusted to 62 kgf / mm ² or less. Sno: A method for producing a surface-treated original plate for a DI can excellent in flange workability of 9.0 or more and excellent in necked-in property.