JP3103268B2 - Method for producing steel sheet for containers with excellent fluting resistance - Google Patents
Method for producing steel sheet for containers with excellent fluting resistanceInfo
- Publication number
- JP3103268B2 JP3103268B2 JP06084283A JP8428394A JP3103268B2 JP 3103268 B2 JP3103268 B2 JP 3103268B2 JP 06084283 A JP06084283 A JP 06084283A JP 8428394 A JP8428394 A JP 8428394A JP 3103268 B2 JP3103268 B2 JP 3103268B2
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- Japan
- Prior art keywords
- steel sheet
- less
- containers
- temperature
- resistance
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
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、耐フルーティング性に
優れた容器用鋼板の製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a steel sheet for containers having excellent fluting resistance.
【０００２】[0002]
【従来の技術】容器用鋼板を缶胴（円型）に成形したと
き部分的に凹みが生じ難い、いわゆる耐フルーティング
性に優れた容器用鋼板の製造方法としては、一般に用い
られている金属組成を有する容器用鋼板をバッチ型焼鈍
により軟化処理して製造することが知られている。又、
特開昭６３−３３５２２号には過時効パターンのヒート
サイクルで連続焼鈍を施すことによりＴ−３以下の表面
処理用原板を製造することが開示されている。2. Description of the Related Art As a method for producing a container steel sheet excellent in so-called fluting resistance, it is difficult to form a partial depression when a steel sheet for a container is formed into a can body (circular shape). It is known that a steel sheet for a container having a composition is softened by batch-type annealing. or,
Japanese Patent Application Laid-Open No. 63-33522 discloses a method of producing a surface treatment sheet having a size of T-3 or less by performing continuous annealing in a heat cycle of an overaging pattern.
【０００３】[0003]
【発明が解決しようとする課題】ところが、上記のごと
き前者の製造方法によれば、バッチ型焼鈍による軟化処
理であり焼鈍開始から終了までの焼鈍工程で約70時間と
長時間を要し、生産性が極めて低いという課題がある。
又、後者の製造法によると、鋼板中の固溶Ｃ量の低減が
十分にできず、耐フルーティング性に優れた容器用鋼板
が製造できない等の課題がある。本発明はこのような課
題を有利に解決するためなされたものであり、一般に用
いられている金属組成を有する容器用鋼板をバッチ型焼
鈍によることなく連続焼鈍により短時間熱処理によって
軟化処理・固溶Ｃ量の低減をはかるとともにトータル圧
下率で高圧下調質圧延によって耐フルーティング性を向
上することを目的とするものである。However, according to the former manufacturing method as described above, the softening treatment is performed by batch-type annealing, and the annealing process from the start to the end of the annealing requires a long time of about 70 hours, and the production is difficult. There is a problem that the property is extremely low.
Further, according to the latter manufacturing method, there is a problem that the amount of solid solution C in the steel sheet cannot be sufficiently reduced, and a steel sheet for containers excellent in fluting resistance cannot be manufactured. The present invention has been made to advantageously solve such problems, and a steel sheet for a container having a generally used metal composition is softened and solid-dissolved by a short-time heat treatment by continuous annealing without using batch annealing. It is an object of the present invention to reduce the carbon content and to improve the fluting resistance by high-pressure temper rolling at a total reduction ratio.
【０００４】[0004]
【課題を解決するための手段】本発明の特徴とするとこ
ろは、Ｃ：0.01〜0.05％、Si：0.034 ％以下、Mn：0.15
〜0.35％、Ｐ：0.015 ％以下、Ｓ：0.023 ％以下、Al：
0.055 〜0.085 ％、Ｎ：0.004 ％以下、残Fe及び不純物
からなる鋼スラブを950 〜1250℃に加熱して熱間圧延を
施し、捲取温度650 〜700 ℃で捲取り、次いで、冷間圧
延後の連続焼鈍で均熱温度660 〜720 ℃で焼鈍を施した
後、３〜20℃／秒の徐冷冷却速度で650〜690 ℃まで冷
却し、引き続き60〜200 ℃／秒の急冷冷却速度で200 〜
300 ℃まで冷却し、次いで、320 〜450 ℃で30〜100 秒
の過時効処理を施し、結晶粒内の炭化物を多く生成させ
た後、トータル圧下率1.8 〜5.0 ％の調質圧延を施すこ
とを特徴とする短時間熱処理による耐フルーティング性
に優れた容器用鋼板の製造方法に関するものである。The features of the present invention are as follows: C: 0.01 to 0.05%, Si: 0.034% or less, Mn: 0.15%
~ 0.35%, P: 0.015% or less, S: 0.023% or less, Al:
A steel slab consisting of 0.055 to 0.085%, N: 0.004% or less, the remaining Fe and impurities is heated to 950 to 1250 ° C, subjected to hot rolling, wound up at a winding temperature of 650 to 700 ° C, and then cold rolled. After annealing at a soaking temperature of 660 to 720 ° C. in the subsequent continuous annealing, it is cooled to 650 to 690 ° C. at a slow cooling rate of 3 to 20 ° C./sec, and then rapidly cooled at a rate of 60 to 200 ° C./sec. 200 ~
After cooling to 300 ° C, it is subjected to an overage treatment at 320 to 450 ° C for 30 to 100 seconds to generate a large amount of carbide in the crystal grains, and then a refining with a total reduction of 1.8 to 5.0%. The present invention relates to a method for producing a steel sheet for containers excellent in fluting resistance by short-time heat treatment, which is characterized by rolling.
【０００５】[0005]
【作用】上記のごとき鋼組成としての特徴は、Alの含有
量を0.055 〜0.085 ％と高含有量とし、又、Ｎ含有量を
0.004 ％以下と低含有量とし、鋼スラブ加熱時にAlＮの
析出を促進し後の熱間圧延により十分なるAlＮの析出を
施し、固溶Ｎを低減することによって結晶粒を成長させ
鋼板を軟質化するとともに、耐フルーティング性を向上
するものである。なお、前記Al量の下限は0.055 ％が好
ましくＮ量は低い程好ましいものである。また、Ｃ、Mn
量としては、容器用鋼板としての強度、硬度等を確保す
ることから上記範囲で十分である。The above steel composition is characterized by a high Al content of 0.055 to 0.085% and a high N content.
Low content of 0.004% or less, promotes precipitation of AlN during heating of steel slab, provides sufficient AlN precipitation by hot rolling afterwards, reduces solid solution N, grows crystal grains and softens steel sheet In addition, the fluting resistance is improved. The lower limit of the Al content is preferably 0.055%, and the lower the N content, the more preferable. Also, C, Mn
The amount is sufficient in the above range to ensure the strength, hardness, and the like of the steel sheet for a container.
【０００６】このような組成の鋼スラブの加熱温度とし
ては、低温加熱によってAlＮの析出を促進するものであ
り950 〜1250℃で十分なるAlＮの析出促進が可能である
が、特に950 〜1100℃と低温域が好ましい。このように
して加熱した鋼スラブを熱間圧延し捲取温度650 〜700
℃と若干低温で捲取ることによって巨大セメンタイトの
生成を防止するとともに、上記スラブの低温加熱による
AlＮ析出促進作用で必要十分なAlＮ析出を達成するもの
である。The heating temperature of the steel slab having such a composition is such that the precipitation of AlN is promoted by heating at a low temperature and the precipitation of AlN can be sufficiently promoted at 950 to 1250 ° C., but especially 950 to 1100 ° C. And a low temperature range is preferred. The steel slab heated in this manner is hot-rolled to a winding temperature of 650 to 700.
The formation of giant cementite is prevented by winding at a temperature as low as ℃, and the slab is heated at a low temperature.
The necessary and sufficient AlN precipitation is achieved by the AlN precipitation promoting action.
【０００７】次いで、上記のごとく圧延した熱間圧延鋼
板（帯）を冷間圧延により冷延鋼板（帯）とし、この鋼
板を連続焼鈍で熱処理を施す。まず、660 〜720 ℃に加
熱し、この温度で数十秒均熱して再結晶させた後、3 〜
20℃の徐冷冷却速度で650 〜690 ℃冷却することによっ
て鋼中にセメンタイトの核を作り易くする。更にこの温
度から60〜200 ℃の急冷冷却速度で冷却し、鋼板温度を
200 〜300 ℃まで冷却することによってセメンタイトの
核を生成せしめる。この熱処理は耐フルーティング性に
大きな影響を及ぼすものである。即ち、急冷によって20
0 〜300 ℃に鋼板を冷却するものであるが、300 ℃未
満、特に250 ℃未満にすることによって耐フルーティン
グ性がより向上し、又、下限としては低温にする程耐フ
ルーティング性は向上するが冷却後の鋼帯コイル内の温
度バラツキが大きくなり且つ炉内通板性も悪化すること
があるので200 ℃を下限とすることが好ましい。又、冷
却速度としては上記のごとく60〜200 ℃／秒であるが、
60℃／秒未満ではセメンタイトの核生成が不十分であ
り、耐フルーティング性のを維持することが困難にな
り、より急速冷却すればセメンタイトの核生成が多くな
り耐フルーティング性も向上するが、コイル内温度のバ
ラツキも考慮すると上限は200 ℃／秒が好ましい。Next, the hot-rolled steel sheet (band) rolled as described above is formed into a cold-rolled steel sheet (band) by cold rolling, and this steel sheet is subjected to heat treatment by continuous annealing. First, heat to 660 to 720 ° C, soak at this temperature for several tens of seconds to recrystallize,
Cooling at 650-690 ° C at a slow cooling rate of 20 ° C facilitates the formation of cementite nuclei in steel. The steel sheet is further cooled from this temperature at a rapid cooling rate of 60 to 200 ° C to reduce the steel sheet temperature.
Cooling to 200-300 ° C produces cementite nuclei. This heat treatment has a great effect on the fluting resistance. That is, 20
The steel sheet is cooled to 0 to 300 ° C, but the fluting resistance is improved by lowering the temperature to less than 300 ° C, especially less than 250 ° C. However, it is preferable to set the lower limit to 200 ° C. because the temperature variation in the steel strip coil after cooling may increase and the in-furnace passability may deteriorate. The cooling rate is 60 to 200 ° C./sec as described above,
At a rate of less than 60 ° C./sec, nucleation of cementite is insufficient, and it is difficult to maintain fluting resistance. If cooled more rapidly, nucleation of cementite increases and fluting resistance improves. The upper limit is preferably 200 ° C./sec in consideration of the variation in the coil temperature.
【０００８】次に、このように急冷した鋼板を320 〜45
0 ℃に昇温し、30〜100 秒保持する過時効処理を施し、
鋼中の固溶Ｃ量を減少させ炭化物密度を高くし、結晶粒
内の炭化物を多くして、後の調質圧延において可動転位
を多く導入するものである。この熱処理も耐フルーティ
ング性に大きな影響を及ぼすものである。即ち、上記の
ごとく鋼板昇温温度が450 ℃を超えると、析出したセメ
ンタイトの核が再固溶して消失することから短時間の熱
処理で過時効処理が困難となり生産性を低下する等の悪
影響があり好ましくない。又、320 ℃未満であると固溶
Ｃ量を減少させる等の効果がほとんど期待できない。
又、上記保持時間は長い程耐フルーティング性は向上す
るが、生産性、設備上の制約から100 秒が好ましく、30
秒未満になると過時効効果が減少するので好ましくな
い。[0008] Next, the steel sheet thus quenched is cooled to 320-45.
The temperature is raised to 0 ° C and overaged for 30 to 100 seconds.
The purpose is to reduce the amount of solid solution C in steel, increase the carbide density, increase the amount of carbide in the crystal grains, and introduce a lot of mobile dislocations in the subsequent temper rolling. This heat treatment also has a significant effect on the fluting resistance. That is, as described above, when the heating temperature of the steel sheet exceeds 450 ° C., the precipitated cementite nucleus re-dissolves and disappears. Is not preferred. On the other hand, if the temperature is lower than 320 ° C., little effect such as reduction of the amount of solid solution C can be expected.
Further, the longer the holding time, the better the fluting resistance. However, it is preferably 100 seconds because of productivity and equipment limitations.
If the time is less than seconds, the overaging effect is undesirably reduced.
【０００９】このようにして、連続焼鈍により熱処理し
た冷延鋼板（帯）を調質圧延するものであるが、圧下率
としてはトータル圧下率で1.8 〜5.0 ％の調質圧延を施
す。即ち、容器用鋼板は板厚が薄く調質圧延スタンドは
複数スタンド（一般的には２スタンド）によって連続的
に圧延するものであり、全スタンドの圧下率、つまりト
ータル圧下率で1.8 〜5.0 ％の調質圧延を施すものであ
る。上記連続焼鈍による熱処理で鋼中の炭化物密度が高
くなっているので、調質圧延によって可動転位が多く導
入でき時効後の降伏点伸びが小さくなって耐フルーティ
ング性が著しく向上するものであり、トータル圧下率が
1.8 ％未満では可動転位を多く導入できず、耐フルーテ
ィング性もそれ程改善できず、5.0 ％超のトータル圧下
率では、加工硬化により硬くなり加工が困難になるの
で、上限は5.0％以下とすることが好ましい。このよう
に本発明においては、結晶粒内炭化物を多く生成させる
ことにより、調質圧延で可動転位を多く導入せしめ、従
来の過時効処理では達成し得なかった短時間で優れた耐
フルーティング性を有する容器用鋼板を製造することが
できるものである。In this way, the cold-rolled steel sheet (band) heat-treated by continuous annealing is subjected to temper rolling, and the temper rolling is performed with a total reduction of 1.8 to 5.0% in terms of a reduction ratio. That is, the steel sheet for containers has a small thickness and the temper rolling stands are continuously rolled by a plurality of stands (generally two stands), and the rolling reduction of all stands, that is, 1.8 to 5.0% in total rolling reduction. Temper rolling. Since the carbide density in the steel is increased by the heat treatment by the continuous annealing, a large number of mobile dislocations can be introduced by temper rolling, the yield point elongation after aging is reduced, and the fluting resistance is significantly improved, Total rolling reduction
If it is less than 1.8%, a large amount of mobile dislocations cannot be introduced, and the fluting resistance cannot be improved so much. If the total draft is more than 5.0%, the work hardens due to work hardening, making it difficult to work. Therefore, the upper limit is made 5.0% or less. Is preferred. As described above, in the present invention, by generating a large amount of carbides in the crystal grains, a large number of mobile dislocations are introduced by the temper rolling, and the excellent fluting resistance in a short time which cannot be achieved by the conventional overaging treatment. Can be produced.
【００１０】このような耐フルーティング性に優れた容
器用鋼板は例えば、乾電池外筒等に有効に用いることが
できる。[0010] Such a steel sheet for a container having excellent fluting resistance can be effectively used, for example, for a battery outer cylinder.
【００１１】[0011]
【実施例】次に、本発明の実施例を比較例とともに挙げ
る。Next, examples of the present invention will be described together with comparative examples.
【表１】 上記のごとく、熱延工程を経た鋼板（帯）を下記のごと
く冷延工程で容器用鋼板を製造した。[Table 1] As described above, a steel sheet (belt) having undergone the hot rolling step was subjected to a cold rolling step as described below to produce a steel sheet for a container.
【表２】 [Table 2]
【表３】 注１ 調質圧延後、板厚0.25mmの容器用鋼板を製造し
た。 注２ フルーティングの有無は、上記のごとく製造した
容器用鋼板を直径35mm、長さ100 mmの円筒（缶胴）を通
常の成形工程で50個成形し、凹みが発生した円筒数を表
示した。[Table 3] * 1 After temper rolling, a 0.25 mm thick container steel plate was manufactured. Note 2 The presence or absence of fluting is indicated by the number of cylinders with dents formed by forming 50 cylinders (can bodies) with a diameter of 35 mm and a length of 100 mm from the steel plate for containers manufactured as described above in the normal molding process. .
【００１２】[0012]
【発明の効果】かくすることにより、本発明は短時間で
耐フルーティング性に優れた容器用鋼板が製造でき、生
産性を著しく向上することができる。又、耐フルーティ
ング性も従来の製造法に比べ、確実に向上させることが
でき工業的に大きな効果を泰することができる等の優れ
た効果が得られるものである。As described above, according to the present invention, a steel sheet for containers having excellent fluting resistance can be manufactured in a short time, and productivity can be remarkably improved. Further, the fluting resistance can be improved more reliably than conventional manufacturing methods, and excellent effects such as great industrial effects can be obtained.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 野村 芳一 愛知県東海市東海町５−３ 新日本製鐵 株式会社名古屋製鐵所内 (56)参考文献 特開 昭61−26725（ＪＰ，Ａ) 特開 平４−327（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 9/46,8/02 C22C 38/00 - 38/60 ────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Yoshikazu Nomura 5-3 Tokai-cho, Tokai-shi, Aichi Prefecture Nippon Steel Corporation Nagoya Works (56) References JP-A-61-26725 (JP, A) JP-A-4-327 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C21D 9/46, 8/02 C22C 38/00-38/60
Claims (1)
n：0.15〜0.35％、Ｐ：0.015％以下、Ｓ：0.023 ％以
下、Al：0.055 〜0.085 ％、Ｎ：0.004 ％以下、残Fe及
び不純物からなる鋼スラブを950 〜1250℃に加熱して熱
間圧延を施し、捲取温度650 〜700 ℃で捲取り、次い
で、冷間圧延後の連続焼鈍で均熱温度660 〜720 ℃で焼
鈍を施した後、３〜20℃／秒の徐冷冷却速度で650 〜69
0 ℃まで冷却し、引き続き60〜200 ℃／秒の急冷冷却速
度で200 〜300 ℃まで冷却し、次いで、320 〜450 ℃で
30〜100 秒の過時効処理を施し、結晶粒内の炭化物を多
く生成させた後、トータル圧下率1.8 〜5.0 ％の調質圧
延を施すことを特徴とする短時間熱処理による耐フルー
ティング性に優れた容器用鋼板の製造方法。1. C: 0.01-0.05%, Si: 0.034% or less, M
n: 0.15 to 0.35%, P: 0.015% or less, S: 0.023% or less, Al: 0.055 to 0.085%, N: 0.004% or less, steel slab consisting of remaining Fe and impurities is heated to 950 to 1250 ° C. Cold rolling, winding at a winding temperature of 650-700 ° C., and continuous annealing after cold rolling, annealing at a soaking temperature of 660-720 ° C., and then gradually cooling at 3-20 ° C./sec. 650-69 at speed
Cool to 0 ° C, then cool to 200-300 ° C at a rapid cooling rate of 60-200 ° C / s, then at 320-450 ° C.
An overage treatment of 30 to 100 seconds is performed to increase the amount of carbide in the crystal grains.
A method for producing a steel sheet for a container having excellent fluting resistance by short-time heat treatment, wherein the steel sheet is subjected to temper rolling at a total draft of 1.8 to 5.0% after being formed .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP06084283A JP3103268B2 (en) | 1994-04-22 | 1994-04-22 | Method for producing steel sheet for containers with excellent fluting resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP06084283A JP3103268B2 (en) | 1994-04-22 | 1994-04-22 | Method for producing steel sheet for containers with excellent fluting resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07292419A JPH07292419A (en) | 1995-11-07 |
| JP3103268B2 true JP3103268B2 (en) | 2000-10-30 |
Family
ID=13826142
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP06084283A Expired - Lifetime JP3103268B2 (en) | 1994-04-22 | 1994-04-22 | Method for producing steel sheet for containers with excellent fluting resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3103268B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03241021A (en) * | 1990-02-20 | 1991-10-28 | Murata Mach Ltd | Spinning equipment |
| JPH03241020A (en) * | 1990-02-20 | 1991-10-28 | Murata Mach Ltd | Spinning equipment |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE60043087D1 (en) * | 1999-04-20 | 2009-11-19 | Nippon Steel Corp | STAHLBLECH FOR ULTRADÜNNE CANS WITH OUTSTANDING ANTI-WRINKLE PROPERTIES AND METHOD FOR THE PRODUCTION THEREOF |
| CN110724884B (en) * | 2019-10-10 | 2020-11-27 | 柳州钢铁股份有限公司 | Manufacturing method of low-cost cold-rolled high-strength steel for goods shelves |
| CN110699608B (en) * | 2019-10-10 | 2020-11-27 | 柳州钢铁股份有限公司 | Low-cost cold-rolled high-strength steel for goods shelves |
| CN112126864A (en) * | 2020-09-09 | 2020-12-25 | 山东钢铁集团日照有限公司 | Production method of cold-rolled steel plate for microwave oven box |
-
1994
- 1994-04-22 JP JP06084283A patent/JP3103268B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03241021A (en) * | 1990-02-20 | 1991-10-28 | Murata Mach Ltd | Spinning equipment |
| JPH03241020A (en) * | 1990-02-20 | 1991-10-28 | Murata Mach Ltd | Spinning equipment |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07292419A (en) | 1995-11-07 |
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