JP4283574B2 - Steel plate for high age-hardening containers with excellent canability and method for producing the same - Google Patents
Steel plate for high age-hardening containers with excellent canability and method for producing the same Download PDFInfo
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【０００１】
【発明の属する技術分野】
本発明は、缶詰及び飲料缶等に用いられる錫メッキ鋼板、クロムメッキ鋼板、フィルムラミネート鋼板等の容器用鋼板の原板となる製缶性に優れた容器用高強度鋼板及びその製造方法に関するものである。
【０００２】
【従来の技術】
【特許文献１】
特開平２−１１８０２５号公報
【特許文献２】
特開平９−１５７７５７号公報
【０００３】
２ピース容器用鋼板は絞り加工を受けるため、ｒ値が大きくならねばならず、箱焼鈍で仕上げたＴ−１、Ｔ−２、Ｔ−３の軟質ブリキが使われることが多かった。しかしながら、このような鋼板はΔｒ値が大きくなるなどの欠点を含んでいるほか、生産効率が低いため鋼板コストも高くなるという課題を持っていた。これに対し、特開平２−１１８０２５号公報では、極低炭素鋼板を用いた連続焼鈍を用い、生産効率が高く、かつ、これまでのｒ値を確保しつつΔｒを低くする技術が提案されている。しかしながら、強度確保のために多量のＮを添加しているため伸びが低くなること、更に高いｒ値の要求に対しては高Ｎ添加では対応が困難であるという課題がある。一方で、特開平９−１５７７５７号公報では、低Ｎの極低炭素鋼板についての技術が提案されているが、Ｎの時効硬化を利用できないため、加工性を犠牲にして２次冷延で高圧下を行わない限りＤＲ−９のような高い強度の鋼板を製造することはできない。
【０００４】
【発明が解決しようとする課題】
本発明は、低Ｎ添加でＮの時効硬化を確保し、高い製缶性を確保しつつ、ＤＲ−８からＤＲ−１０相当の高い強度を持つ鋼板とその製造方法を達成することを目的とする。
【０００５】
【課題を解決するための手段】
上記の目的を達成すべく、化学成分、特にＮとＭｎの相互作用について鋭意検討を重ねた結果、Ｎに与えるＭｎの作用を見出すことで、ＮとＡｌ、Ｍｎの関係式にて低Ｎ添加でもＮの時効硬化による強化を利用し、製缶性に優れた容器用高強度鋼板を開発するに至った。
【０００６】
その要旨は、下記の通りである。
（１） 質量％で、
Ｃ ：０．００６％以下、
Ｓｉ：０．０４％以下、
Ｍｎ：０．５０％超、０．６０％以下、
Ｐ ：０．０２％以下
Ｓ ：０．０２％以下
Ａｌ：０．００５％超、０．１％以下、
Ｎ ：０．００２％超、０．０１％以下、
を含有し、更に、
Ｎ×ｅｘｐ（−１３×Ａｌ／Ｍｎ）≧０．００１ （１）
Ｃ＋0.02×Ｍｎ 2 −0.0048×Ｍｎ−0.01×Ｐ≦0.0077 （２）
の式を満たし、かつ残部が鉄および不可避的不純物からなり、Ｈ R ３０Ｔ硬度が72.7以上であることを特徴とする製缶性に優れた高時効硬化容器用鋼板。
（２） 前記（１）に記した鋼の成分において、更にＣａ：０．００５％以下を含有している製缶性に優れた高時効硬化容器用鋼板。
（３） 鋼板に表面処理を施した（１）又は（２）に記載の製缶性に優れた高時効硬化容器用鋼板。
（４）表面処理がクロムめっきまたは錫メッキまたはニッケルめっきである（３）に記載の製缶性に優れた高時効硬化容器用鋼板。
（５） （３）又は（４）に記した鋼板に、更にフィルムラミネート処理をする製缶性に優れた高時効硬化容器用鋼板。
（６） （１）又は（２）に記した鋼に、８５０℃以上の仕上温度で熱間圧延を施し、捲取温度までの平均冷速を１５℃/s以上にて冷却し、５７０℃以下の温度で捲取り、次いで通常の酸洗の後、圧下率を５０〜９８％として一次冷間圧延後、連続焼鈍工程で６００℃以上オーステナイト化温度以下に均熱して再結晶焼鈍を施し、次いで圧下率２０〜４０％の二次冷間圧延を施した製缶性に優れた高時効硬化容器用鋼板の製造方法。
【０００７】
【発明の実施の形態】
本発明は０．００６％以下のＣを含有する鋼にＮとＡｌ、Ｍｎを調整し、更にＳｉ、Ｐ、Ｓを若干量添加、必要に応じてＣａを添加した容器用鋼板である。そして、製缶性を確保するため低Ｎとし、ＡｌＮの析出を制御することで固溶Ｎを確保し、この時効硬化を用いて強度を高めたものである。このとき、Ｎ、Ａｌ、ＭｎはＡｌＮの析出を制御する目的で添加させ、詳細はわからないが、Ｍｎはオーステナイト生成元素であるため、フェライト変態を抑制させることでＡｌＮ析出の抑制に寄与するものと考えている。本発明は以上のような骨子に基づくが、以下に本発明の個々の構成要件について詳細に説明する。
【０００８】
以下に本発明の成分の限定理由について述べる。
Ｃは、深絞り性、延性に大きな影響を与える元素であり、０．００６％を超えるとｒ値、延性とも著しく低減するため、０．００６％以下とする。好ましくは、０．００４超、０．００６％以下のＣは製鋼での成分調整が困難であり、製造コストの増加につながるため０．００４％以下が望ましく、０．００１％未満ではリジングの発生が懸念されるためこれ以上の添加が望ましい。
【０００９】
Ｓｉは、ブリキの耐食性を劣化させるほかに、材質を大きく硬質化する置換型固溶体強化元素であり、延性、加工性を向上させるに好ましくない元素である。そこで、０．０４％を上限とする。
【００１０】
Ｍｎは、本発明において重要な元素である。固溶強化により母材材質を高めるほか、熱延冷却時の変態を抑制することでＡｌＮの生成を抑制し、低いＮにも関わらず固溶Ｎの確保を可能とする。この効果を得るためには０．５％超の添加が必要である．また、０．６％を越えると加工性が劣化する場合があるため０．６％を上限とすることが望ましい。
【００１１】
Ｐは鋼板の強度を上げる元素であるが、成形性、耐食性を害するため、できるだけ低減する。０．０２％以下であれば大きな劣化はないため０．０２％以下とする。
【００１２】
Ｓは鋼中に存在しない方が好ましい元素であり、特に加工性を高めるためには低い方が望ましく上限を０．０２％とする。
【００１３】
Ａｌは、脱酸材として鋼の清浄度を向上させるため添加する。清浄度向上のためには０．００５％超の添加が必要である。但し、０．１％を超える添加はＡｌＮを粗大化させ、Ｎの低減させ、Ｎの時効硬化が得られなくなるため０．１％以下とする。
【００１４】
Ｎは、時効硬化により材料を強化させるために必須な元素であり、この効果を得るためには０．００２％超の添加が必要である。但し、多量の添加は加工性を確保するためには少ない方が良く、０．０１％を越えると著しく加工性が劣化してくるので、０．０１％を上限とする。
【００１５】
Ｃａは、介在物の形態制御に有効であり、薄物鋼板の加工性を良くする事や低温脆性を良くすることが可能である。しかし、過剰に存在すると熱間加工性が悪くなり望ましくないため０．００５％以下とする。
【００１６】
低Ｎで固溶Ｎを確保するためにはＡｌＮの析出制御が重要である。発明者らは鋭意検討した結果、Ｎ、Ａｌの関係加え、オーステナイト生成元素でフェライト変態を抑制するＭｎが析出の抑制に硬化があることを見出し、以下の関係式を導き出すに至った。関係式右辺が０．００１未満ではＮの時効硬化量が不足するため、所定の硬度の確保のために通常に比べ調質圧延を多く取らなくてはならず成形性の低下につながる。
Ｎ×ｅｘｐ（−１３×Ａｌ／Ｍｎ）≧０．００１ （１）
【００１７】
また、加工性を得るためには一定以上のｒ値が必要であり、更にイヤリング性を良くするためにはΔｒ値を０に近づけることが重要だが、これにはＣ添加量を抑える必要がある。加えて結晶粒径を制御することでも加工性が良くなることに繋がるが、Ｍｎ、Ｐの添加量を最適にすることで効果が表れる。以上をふまえて下式（２）で範囲を指定する。
Ｃ＋0.02×Ｍｎ2 −0.0048×Ｍｎ−0.01×Ｐ≦0.0077 （２）
【００１８】
不可避元素としては、例えば、Ｃｕ：０．２％以下、Ｎｉ：０．１５％以下、Ｃｒ：０．１％以下、Ｍｏ：０．０５％以下、Ｃｏ：０．０２％以下、Ｚｎ：０．０２％以下、Ｓｎ：０．０２％以下、Ｎａ：０．０２％以下、Ｂ：０．０００５％以下で含有していても、本発明を逸脱するものではない。
【００１９】
次に製造方法について説明する。
熱延の仕上温度はフェライト粒にひずみが過度に加わり加工性が低下するのを防ぐには熱間圧延を８５０℃以上で行う必要がある。また、高温すぎても焼鈍後の再結晶粒径は必要以上に粗大化するため、９６０℃以下が望ましい。ＡｌＮの生成を抑制するためには熱延仕上から、捲取温度までの平均冷却を１５℃／ｓ以上とすることが必要である。好ましくは、ＡｌＮの抑制を狙うため、７００℃までの平均冷速を５０℃／ｓ以上とすることが望ましい。巻き取り温度については、高温にすれば再結晶や粒成長が促進され、加工性の向上が望まれるが、ＡｌＮの析出を促進するため５７０℃以下とする。
【００２０】
酸洗後の冷間圧延は、圧下率が低いと鋼板の形状矯正が難しくなるため５０％以上とする。また、９８％を超える圧下率で圧延すると、局部延性の劣化が発生することがあるため望ましくない。さらに、加工性を良くするために高ｒ値にしたいため、好ましくは７０％以上９５％以下の範囲が良い。
【００２１】
連続焼鈍温度は低すぎると未再結晶の状態になり硬質化し、逆に高すぎると粒が粗大化するという問題点があるので、６００℃以上オーステナイト温度域以下とする。その後二次冷間圧延を行うが、ＤＲ８〜ＤＲ１０の調質度を得るために、適切な圧下率をとれば良い。ただし、加工性の悪化を防ぐため圧延率は４０％以下とする。
なお、本鋼板のめっきは通常のクロムめっき、錫めっき、ニッケルめっき等のいずれにも適用できる。また、鋼板上やめっき鋼板上にフィルムラミネートを行う用途にも適用できる。
【００２２】
【実施例】
次に本発明を実施例に基づいて説明する。
表１に示す成分の鋼を溶製し、常法に従い連続鋳造でスラブとした。符号Ａ〜Ｒが本発明に従った成分の鋼で、Ａ〜Ｎは式（１）、式（２）とも満たしており、Ｏ〜Ｒは式（１）のみ満たすものである。符号Ｓの鋼はＣ添加量、Ｔ、Ｕ、Ｖの鋼は式（１）を満たしていない。これらの鋼を加熱炉中で１１５０℃以上の温度で加熱し、熱間圧延にて板厚２．２〜３．２ｍｍの熱延鋼板を得た。熱延条件については表２に示す。これに続いて酸洗後、８５％〜９５％の冷間圧延を行い、表２に示す焼鈍温度にて再結晶焼鈍、調質圧延を行った。このとき、Ｂ３は捲取温度と調質圧延が高く本発明の範囲外、Ｃ３は調質圧延が本発明の範囲外、Ｄ３は冷却速度及び調質圧延が本発明の範囲外、Ｆ３は焼鈍温度が本発明の範囲外である。
【００２３】
このようにして得られた鋼板について、硬度を測定（ＨR ３０Ｔ）した。また、ｒ値、Δｒ値の測定を簡易測定法である" モジュールｒ”（StolleCorp. 社製、Module-r Drawability Tester 使用）により行った。結果を表２、図１、図２に示す。図から明らかなように本発明鋼は、比較鋼に比べてｒ値、Δｒ値とも良い特性を示しており、中でも、式（２）も満たすものは更にｒ値が高くなっていることがわかる。
【００２４】
【表１】
【表２】
【発明の効果】
本発明によれば、十分な製缶性を有しかつ、十分な強度を確保した容器用鋼板を製造することが出来る。本発明の方法による鋼板は、従来の鋼板と比較してｒ値が高くかつ面内異方性も低いため、深絞り性や加工性が良く成形時のトラブルが減り歩留も上がるという利点がある。
【図面の簡単な説明】
【図１】 硬さに対するｒ値に及ぼす本発明鋼の効果を示すグラフである。
【図２】 硬さに対するΔｒ値に及ぼす本発明鋼の効果を示すグラフである。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a high-strength steel sheet for containers excellent in canability, which is an original sheet for steel sheets for containers such as tin-plated steel sheets, chrome-plated steel sheets, and film-laminated steel sheets used in cans and beverage cans, and a method for producing the same. is there.
[0002]
[Prior art]
[Patent Document 1]
Japanese Patent Laid-Open No. 2-118025 [Patent Document 2]
Japanese Patent Laid-Open No. 9-157757
Since the steel plate for two-piece containers is subjected to drawing, the r value has to be large, and soft tin plates of T-1, T-2, and T-3 finished by box annealing are often used. However, such a steel sheet has drawbacks such as a large Δr value, and has a problem that the cost of the steel sheet increases due to low production efficiency. On the other hand, Japanese Patent Laid-Open No. 2-11825 proposes a technique that uses continuous annealing using an ultra-low carbon steel plate, has high production efficiency, and lowers Δr while securing the conventional r value. Yes. However, since a large amount of N is added to ensure the strength, there is a problem that elongation is low, and it is difficult to respond to a request for a high r value with high N addition. On the other hand, Japanese Patent Application Laid-Open No. 9-157757 proposes a technique for a low-N ultra-low carbon steel sheet. However, since N age hardening cannot be used, high pressure is applied by secondary cold rolling at the expense of workability. A high strength steel sheet like DR-9 cannot be produced unless the following is performed.
[0004]
[Problems to be solved by the invention]
It is an object of the present invention to achieve a steel sheet having a high strength equivalent to DR-8 to DR-10 and a method for producing the same while ensuring age hardening of N with low N addition and ensuring high canability. To do.
[0005]
[Means for Solving the Problems]
As a result of intensive investigations on the chemical components, especially the interaction between N and Mn, in order to achieve the above-mentioned objective, by finding the action of Mn on N, the addition of low N in the relational expression of N, Al and Mn However, the strengthening by age-hardening of N was utilized to develop a high-strength steel sheet for containers with excellent canability.
[0006]
The summary is as follows.
(1) In mass%,
C: 0.006% or less,
Si: 0.04% or less,
Mn: more than 0.50%, 0.60% or less,
P: 0.02% or less S: 0.02% or less Al: more than 0.005%, 0.1% or less,
N: more than 0.002%, 0.01% or less,
Further,
N × exp (−13 × Al / Mn) ≧ 0.001 (1)
C + 0.02 × Mn 2 −0.0048 × Mn−0.01 × P ≦ 0.0077 (2)
A high age-hardening vessel steel plate excellent in canability, characterized by satisfying the following formula, with the balance being iron and inevitable impurities and having an H R 30T hardness of 72.7 or more .
(2) A steel plate for a high-age-hardening container excellent in canability, further containing Ca: 0.005% or less in the steel component described in (1) .
(3) A steel plate for a high-age hardening container excellent in canability as described in (1) or (2), wherein the steel plate is surface-treated .
(4) The steel plate for high age-hardening containers having excellent canability as described in (3), wherein the surface treatment is chromium plating, tin plating or nickel plating .
(5) A steel plate for a high-age-hardening container excellent in can-making properties, wherein the steel plate described in (3) or (4) is further subjected to film lamination .
(6) The steel described in (1) or (2) is hot-rolled at a finishing temperature of 850 ° C. or higher, and is cooled at an average cooling rate of 15 ° C./s or higher up to the milling temperature. After the usual pickling, and after the normal pickling, after the primary cold rolling with a reduction ratio of 50 to 98%, soaking at a temperature of 600 ° C. or more and austenitizing temperature or less in a continuous annealing step, recrystallization annealing is performed, Subsequently, the manufacturing method of the steel plate for high age hardening containers excellent in the can-making nature which gave the secondary cold rolling of 20-40% of rolling reduction .
[0007]
DETAILED DESCRIPTION OF THE INVENTION
The present invention is a steel plate for containers in which N, Al, and Mn are adjusted to steel containing 0.006% or less of C, and a small amount of Si, P, and S are added, and Ca is added as necessary. And in order to ensure can-making property, it is made low N, solid solution N is ensured by controlling precipitation of AlN, and strength is increased by using this age hardening. At this time, N, Al, and Mn are added for the purpose of controlling the precipitation of AlN, and details are not known, but since Mn is an austenite-generating element, it contributes to the suppression of AlN precipitation by suppressing ferrite transformation. thinking. Although the present invention is based on the above-mentioned outline, the individual components of the present invention will be described in detail below.
[0008]
The reasons for limiting the components of the present invention are described below.
C is an element having a great influence on deep drawability and ductility. If it exceeds 0.006%, the r value and ductility are significantly reduced. Preferably, C of more than 0.004 and 0.006% or less is difficult to adjust the composition in steelmaking, and leads to an increase in production cost, so 0.004% or less is desirable, and if it is less than 0.001%, ridging is generated. Addition beyond this is desirable.
[0009]
Si is a substitutional solid solution strengthening element that hardens the material in addition to deteriorating the corrosion resistance of the tinplate, and is an undesirable element for improving ductility and workability. Therefore, the upper limit is 0.04%.
[0010]
Mn is an important element in the present invention. In addition to increasing the base material material by solid solution strengthening, the formation of AlN is suppressed by suppressing transformation during hot rolling cooling, and solid solution N can be secured despite low N. To obtain this effect, it is necessary to add more than 0.5%. Further, if it exceeds 0.6%, the workability may be deteriorated, so it is desirable to set the upper limit to 0.6%.
[0011]
P is an element that increases the strength of the steel sheet, but is reduced as much as possible because it impairs formability and corrosion resistance. If it is 0.02% or less, there is no significant deterioration, so 0.02% or less.
[0012]
S is an element that is preferably not present in steel, and in order to improve workability, in particular, a lower value is desirable and the upper limit is set to 0.02%.
[0013]
Al is added as a deoxidizer to improve the cleanliness of the steel. In order to improve the cleanliness, it is necessary to add more than 0.005%. However, addition exceeding 0.1% coarsens AlN, reduces N, and age hardening of N cannot be obtained, so it is made 0.1% or less.
[0014]
N is an essential element for strengthening the material by age hardening, and in order to obtain this effect, addition of over 0.002% is necessary. However, a small amount of addition is better in order to ensure workability, and if it exceeds 0.01%, the workability is significantly deteriorated, so 0.01% is made the upper limit.
[0015]
Ca is effective in controlling the form of inclusions, and can improve the workability of thin steel plates and low-temperature brittleness. However, if it exists excessively, the hot workability deteriorates and is not desirable, so the content is made 0.005% or less.
[0016]
In order to secure solid solution N at low N, it is important to control the precipitation of AlN. As a result of intensive studies, the inventors have found that Mn, which suppresses ferrite transformation with an austenite-generating element, has a hardening in suppressing precipitation in addition to the relationship between N and Al, and has led to the following relational expression. If the right side of the relational expression is less than 0.001, the age hardening amount of N is insufficient, so that a large amount of temper rolling must be performed in order to ensure a predetermined hardness, leading to a decrease in formability.
N × exp (−13 × Al / Mn) ≧ 0.001 (1)
[0017]
Further, in order to obtain processability, an r value of a certain value or more is necessary, and in order to further improve the earring property, it is important to bring the Δr value close to 0, but this requires the amount of C to be suppressed. . In addition, control of the crystal grain size leads to improved workability, but an effect can be obtained by optimizing the addition amount of Mn and P. Based on the above, the range is specified by the following formula (2).
C + 0.02 × Mn 2 −0.0048 × Mn−0.01 × P ≦ 0.0077 (2)
[0018]
Inevitable elements include, for example, Cu: 0.2% or less, Ni: 0.15% or less, Cr: 0.1% or less, Mo: 0.05% or less, Co: 0.02% or less, Zn: 0 0.02% or less, Sn: 0.02% or less, Na: 0.02% or less, and B: 0.0005% or less do not depart from the present invention.
[0019]
Next, a manufacturing method will be described.
As for the hot rolling finishing temperature, it is necessary to carry out hot rolling at 850 ° C. or higher in order to prevent the strain from being excessively applied to the ferrite grains and lowering the workability. Moreover, since the recrystallized grain size after annealing becomes larger than necessary even if the temperature is too high, 960 ° C. or lower is desirable. In order to suppress the formation of AlN, it is necessary to set the average cooling from hot-rolling finish to the scraping temperature to 15 ° C./s or more. Preferably, the average cooling rate up to 700 ° C. is 50 ° C./s or more in order to suppress AlN. The coiling temperature is set to 570 ° C. or lower in order to promote the precipitation of AlN, although recrystallization and grain growth are promoted and workability is improved if the coiling temperature is increased.
[0020]
Cold rolling after pickling is made 50% or more because the shape reduction of the steel sheet becomes difficult if the rolling reduction is low. Further, rolling at a rolling reduction exceeding 98% is not desirable because local ductility may be deteriorated. Further, in order to improve the workability, a high r value is desired, and the range of 70% to 95% is preferable.
[0021]
If the continuous annealing temperature is too low, it becomes a non-recrystallized state and hardens, and conversely if too high, the grains become coarse, so the temperature is set to 600 ° C. or more and the austenite temperature range or less. After that, secondary cold rolling is performed, and an appropriate rolling reduction may be taken in order to obtain a refining degree of DR8 to DR10. However, the rolling rate is 40% or less in order to prevent deterioration of workability.
In addition, the plating of this steel plate can be applied to any of ordinary chromium plating, tin plating, nickel plating and the like. Moreover, it is applicable also to the use which performs film lamination on a steel plate or a plated steel plate.
[0022]
【Example】
Next, this invention is demonstrated based on an Example.
Steels having the components shown in Table 1 were melted and slabs were obtained by continuous casting according to a conventional method. Reference signs A to R are steels of the components according to the present invention, A to N satisfy both formula (1) and formula (2), and O to R satisfy only formula (1). The steel of the code | symbol S does not satisfy | fill Formula (1), the steel of C addition amount, T, U, and V. These steels were heated in a heating furnace at a temperature of 1150 ° C. or higher, and hot rolled steel sheets having a thickness of 2.2 to 3.2 mm were obtained by hot rolling. Table 2 shows the hot rolling conditions. Subsequently, after pickling, cold rolling of 85% to 95% was performed, and recrystallization annealing and temper rolling were performed at the annealing temperatures shown in Table 2. At this time, B3 has a high milling temperature and temper rolling, which is outside the scope of the present invention, C3 is temper rolling outside the scope of the present invention, D3 is a cooling rate and temper rolling is outside the scope of the present invention, and F3 is annealed. The temperature is outside the scope of the present invention.
[0023]
The steel sheet thus obtained was measured for hardness (H R 30T). Further, the r value and Δr value were measured by “Module r” (Stolle Corp., using Module-r Drawability Tester), which is a simple measurement method. The results are shown in Table 2, FIG. 1 and FIG. As is clear from the figure, the steel of the present invention shows good characteristics for both the r value and the Δr value compared to the comparative steel, and among them, those satisfying the formula (2) have a higher r value. .
[0024]
[Table 1]
[Table 2]
【The invention's effect】
ADVANTAGE OF THE INVENTION According to this invention, it can manufacture the steel plate for containers which has sufficient can-making property and ensured sufficient intensity | strength. The steel plate according to the method of the present invention has an advantage that the r value is high and the in-plane anisotropy is low as compared with the conventional steel plate, so that deep drawability and workability are good and troubles during forming are reduced and the yield is increased. is there.
[Brief description of the drawings]
FIG. 1 is a graph showing the effect of the steel of the present invention on the r value with respect to hardness.
FIG. 2 is a graph showing the effect of the steel of the present invention on the Δr value with respect to hardness.
Claims (6)
Ｃ ：０．００６％以下、
Ｓｉ：０．０４％以下、
Ｍｎ：０．５０％超、０．６０％以下、
Ｐ ：０．０２％以下
Ｓ ：０．０２％以下
Ａｌ：０．００５％超、０．１％以下、
Ｎ ：０．００２％超、０．０１％以下、
を含有し、更に、
Ｎ×ｅｘｐ（−１３×Ａｌ／Ｍｎ）≧０．００１ （１）
Ｃ＋0.02×Ｍｎ 2 −0.0048×Ｍｎ−0.01×Ｐ≦0.0077 （２）
の式を満たし、かつ残部が鉄および不可避的不純物からなり、Ｈ R ３０Ｔ硬度が72.7以上であることを特徴とする製缶性に優れた高時効硬化容器用鋼板。% By mass
C: 0.006% or less,
Si: 0.04% or less,
Mn: more than 0.50%, 0.60% or less,
P: 0.02% or less S: 0.02% or less Al: more than 0.005%, 0.1% or less,
N: more than 0.002%, 0.01% or less,
Further,
N × exp (−13 × Al / Mn) ≧ 0.001 (1)
C + 0.02 × Mn 2 −0.0048 × Mn−0.01 × P ≦ 0.0077 (2)
A high age-hardening vessel steel plate excellent in canability, characterized by satisfying the following formula, with the balance being iron and inevitable impurities and having an H R 30T hardness of 72.7 or more .
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