JPH0873943A - Production of soft tin plate and soft steel plate for tes - Google Patents
Production of soft tin plate and soft steel plate for tesInfo
- Publication number
- JPH0873943A JPH0873943A JP21290994A JP21290994A JPH0873943A JP H0873943 A JPH0873943 A JP H0873943A JP 21290994 A JP21290994 A JP 21290994A JP 21290994 A JP21290994 A JP 21290994A JP H0873943 A JPH0873943 A JP H0873943A
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- Prior art keywords
- soft
- range
- temp
- continuous annealing
- less
- Prior art date
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、そのテンパー度がＴ３
以下の軟質なぶりきおよびＴＦＳ用鋼板の製造方法に関
する。BACKGROUND OF THE INVENTION The present invention has a temper degree of T3.
The following relates to a method for manufacturing a soft tin plate and a steel sheet for TFS.
【０００２】[0002]
【従来の技術】ぶりきやＴＦＳは、ロックウェル硬さ試
験（ＨＲ３０Ｔ）で測定した硬度をもとにＴ１からＴ６
までの６段階のテンパー度により分類されおり、一般に
はテンパー度がＴ１からＴ３までの軟質材は箱焼鈍法に
よって、またテンパー度がＴ４からＴ６の硬質材は主と
して連続焼鈍法によって製造されている。2. Description of the Related Art Tinplate and TFS are measured from T1 to T6 based on the hardness measured by Rockwell hardness test (HR30T).
Are classified according to the 6-degree tempering degree. Generally, soft materials with tempering degrees from T1 to T3 are manufactured by the box annealing method, and hard materials with tempering degrees from T4 to T6 are mainly manufactured by the continuous annealing method. .
【０００３】近年、生産性が著しく劣り、しかもコイル
長手方向や幅方向に材質均一性の悪い箱焼鈍法に代わっ
て、連続焼鈍法による軟質材の製造が検討されている。
通常の低炭素鋼を用いて従来の連続焼鈍法で製造する
と、焼鈍後の急速冷却により鋼中に固溶Ｃが多量に残る
ため、焼付塗装時に歪み時効を起こし、その後の製缶な
どの加工時にフルーティングやストレッチャーストレイ
ンなどの成形不良が生じる。In recent years, the production of soft materials by continuous annealing has been studied in place of the box annealing method, which is extremely inferior in productivity and has poor material uniformity in the longitudinal and width directions of the coil.
When manufactured by the conventional continuous annealing method using ordinary low carbon steel, a large amount of solute C remains in the steel due to rapid cooling after annealing, which causes strain aging during baking coating and subsequent processing such as can making. Sometimes molding defects such as fluting and stretcher strain occur.
【０００４】そこで連続焼鈍法によって加工用の軟質材
を製造するには、焼鈍後の固溶ＣやＮ量を極力低減し、
焼付塗装時の歪み時効による降伏点伸びの回復を抑制す
る必要がある。経験的には、この降伏点伸びの回復を５
％以内、望ましくは４％以内に抑制すれば製缶時などに
フルーティングやストレッチャーストレインなどの問題
が生じないことがわかっている。焼鈍後の固溶ＣやＮ量
を極力低減する軟質材の製造方法として、例えば特開平
５−２６３１４３号公報には、極低Ｃ鋼にＴｉ、Ｎｂ、
Ｂなどの炭窒化物形成元素を添加して固溶ＣやＮ量を低
減する方法が、また特開昭６０−６７６２７号公報に
は、通常の低炭素鋼を過時効処理帯を設けた連続焼鈍ラ
インで焼鈍して固溶Ｃ量を低減する方法が提案されてい
る。Therefore, in order to manufacture a soft material for processing by the continuous annealing method, the amount of solid solution C and N after annealing is reduced as much as possible,
It is necessary to suppress recovery of yield point elongation due to strain aging during baking coating. Empirically, the recovery of the yield point elongation is 5
It has been found that if the content is suppressed to within%, preferably 4%, problems such as fluting and stretcher strain will not occur during can making. As a method of manufacturing a soft material that reduces the amount of solid solution C and N after annealing as much as possible, for example, in Japanese Patent Laid-Open No. 263143/1993, Ti, Nb, and
A method of adding a carbonitride-forming element such as B to reduce the amount of solid solution C and N, and JP-A-60-67627 discloses a continuous method in which ordinary low carbon steel is provided with an overaging zone. A method for reducing the amount of solute C by annealing in an annealing line has been proposed.
【０００５】[0005]
【発明が解決しようとする課題】しかしながら特開平５
−２６３１４３号公報に記載される方法では、極低Ｃ鋼
を用いているためコスト高となる。また特開昭６０−６
７６２７号公報に記載される方法では、低炭素鋼を用い
ているが、熱延後高温巻取りしているためコイル長手方
向や幅方向にカーバイド形態やＡｌＮの析出状態が不均
一となり、その結果最終製品のコイル長手方向や幅方向
における材質の均一性が悪い。さらに連続焼鈍において
Ａ1 変態点以上の高温加熱を行っているため、缶用材料
のような板厚の薄い鋼板ではヒートバックルなどの通板
トラブルが発生し易い。[Patent Document 1] Japanese Unexamined Patent Publication No.
In the method described in Japanese Patent Laid-Open No. 263143, the cost is high because extremely low C steel is used. In addition, JP-A-60-6
In the method described in Japanese Patent No. 7627, low carbon steel is used, but since it is hot rolled after hot rolling, the form of carbide and the precipitation state of AlN become non-uniform in the coil longitudinal direction and width direction, and as a result The uniformity of the material in the longitudinal and width directions of the final product is poor. Furthermore, since high-temperature heating above the A 1 transformation point is performed in continuous annealing, a steel plate having a thin plate thickness such as a can material is likely to cause a threading problem such as a heat buckle.
【０００６】本発明はこのような問題を解決するために
なされたもので、低コストで、コイル長手方向や幅方向
に硬度などの材質の均一性に優れ、焼鈍時の通板トラブ
ルも起きず、しかも製缶などの加工時にフルーティング
などの成形不良が起こらない連続焼鈍法によるＴ３以下
の軟質なぶりきおよびＴＦＳ用鋼板の製造方法を提供す
ることを目的とする。The present invention has been made in order to solve such a problem and is low in cost, excellent in the uniformity of the material such as hardness in the longitudinal direction and width direction of the coil, and does not cause the trouble of passing the sheet during annealing. Moreover, it is an object of the present invention to provide a method for manufacturing a soft tint of T3 or less and a steel sheet for TFS by a continuous annealing method in which a forming defect such as fluting does not occur during the processing of cans and the like.
【０００７】[0007]
【課題を解決するための手段】上記課題は、重量％で、
Ｃ：０．０５０〜０．０８５、Ｍｎ：０．０５〜０．６
０、Ｐ：０．０２以下、Ｓ：０．０２以下、ＳｏｌＡ
ｌ：０．１０以下、かつＡｌとＮの原子比Ａｌ／Ｎ≧１
５となるようにＮを含む鋼を用い、熱間圧延後５５０℃
以上６２０℃未満の温度域で巻取り、次いで冷間圧延後
連続焼鈍法により６５０℃以上Ａ1 変態点未満の温度域
に加熱し、その後３０℃／ｓ以上の冷却速度で３５０℃
以上４５０℃以下の温度域まで冷却し、その温度で３０
秒以上の過時効処理を行うぶりきおよびＴＦＳ用鋼板の
製造方法によって解決される。[Means for Solving the Problems] The above-mentioned problems, in% by weight,
C: 0.050 to 0.085, Mn: 0.05 to 0.6
0, P: 0.02 or less, S: 0.02 or less, SolA
l: 0.10 or less, and atomic ratio of Al and N Al / N ≧ 1
Steel containing N so that it becomes 5 and 550 ° C after hot rolling
Winding in the temperature range above 620 ° C., then by cold rolling followed by continuous annealing, heating to a temperature range above 650 ° C. and below the A 1 transformation point, then 350 ° C. at a cooling rate of 30 ° C./s or above
Cool down to a temperature range above 450 ℃
The problem is solved by a method of manufacturing a tin plate and a steel sheet for TFS, which is performed by overaging for more than a second.
【０００８】また加工時に発生するフルーティングなど
の成形不良に対しては、Ｃ量を０．０６０〜０．０８０
重量％に制御することがより好ましい。For defective molding such as fluting that occurs during processing, the C content is 0.060 to 0.080.
It is more preferable to control to the weight%.
【０００９】[0009]
【作用】以下に本発明の成分および製造条件の限定理由
について述べる。The reasons for limiting the components and production conditions of the present invention will be described below.
【００１０】Ｃは材質や焼付塗装時の歪み時効に対して
重要な役割を演じる元素である。そこでＣ以外の成分元
素量や製造条件を前記本発明の範囲内で一定とし、Ｃ量
のみを変化させたサンプルを作成し、これらサンプルに
焼付塗装に相当する熱処理を施した後、引張試験を行っ
て降伏点伸びを測定して、Ｃ量と降伏点伸びの関係を調
査した。結果を図１に示す。Ｃ量が０．０５０〜０．０
８５重量％の範囲内にあれば、焼付塗装後の降伏点伸び
を５％以内に抑えられ、前記のごとくフルーティングな
どの成形不良の問題を回避できる。したがってＣ量を
０．０５０〜０．０８５重量％の範囲に限定する。さら
に好ましくはＣ量を０．０６０〜０．０８０重量％の範
囲内に制御すると、焼付塗装後の降伏点伸びを４％以内
に抑えられ、フルーティングなどの成形不良に対してよ
り有利になる。C is an element that plays an important role in the material and strain aging during baking coating. Therefore, the amount of the constituent elements other than C and the manufacturing conditions are kept constant within the range of the present invention, samples having different amounts of C are prepared, and the samples are subjected to heat treatment corresponding to baking coating, and then subjected to a tensile test. The yield point elongation was measured and the relationship between the C content and the yield point elongation was investigated. The results are shown in Fig. 1. C amount is 0.050 to 0.0
Within the range of 85% by weight, the yield point elongation after baking coating can be suppressed within 5%, and the problem of defective molding such as fluting can be avoided as described above. Therefore, the C content is limited to the range of 0.050 to 0.085% by weight. More preferably, if the C content is controlled within the range of 0.060 to 0.080% by weight, the yield point elongation after baking coating can be suppressed within 4%, which is more advantageous for molding defects such as fluting. .
【００１１】Ｍｎは０．０５重量％未満だと熱間脆性の
問題が起こるのでそれ以上にする必要がある。また０．
６０重量％を越えて含まれると硬質化し、本発明法によ
ってＴ３以下の軟質材を製造することができなくなる。
したがってＭｎ量を０．０５〜０．６０重量％の範囲に
限定する。If Mn is less than 0.05% by weight, the problem of hot embrittlement occurs, so it is necessary to increase it. In addition, 0.
If it is contained in an amount of more than 60% by weight, it becomes hard and it becomes impossible to produce a soft material having T3 or less by the method of the present invention.
Therefore, the amount of Mn is limited to the range of 0.05 to 0.60% by weight.
【００１２】Ｐは０．０２重量％を越えて含まれると硬
質化するとともに、耐食性も劣化する。したがってＰ量
を０．０２重量％以下に限定する。If P is contained in an amount of more than 0.02% by weight, it hardens and the corrosion resistance deteriorates. Therefore, the amount of P is limited to 0.02% by weight or less.
【００１３】Ｓは０．０２重量％を越えて含まれると熱
間脆性の問題が起こるとともに、加工性も劣化する。し
たがってＳ量を０．０２重量％以下に限定する。If S is contained in an amount of more than 0.02% by weight, the problem of hot brittleness occurs and the workability also deteriorates. Therefore, the amount of S is limited to 0.02% by weight or less.
【００１４】Ａｌ、Ｎも本発明の重要な構成要件の一つ
である。熱延巻取り時にＡｌＮとしてＮを析出させない
と、連続焼鈍時に微細なＡｌＮの析出が起こり結晶粒の
成長を阻害し、その結果組織は細粒になり硬質化する。
一方ＡｌＮの析出を促進するために高温巻取りを行う
と、前記したようにコイル長手方向や幅方向に硬度など
の材質の均一性が悪化する。そこで低温巻取りでＡｌＮ
を析出させる条件をＡｌとＮの原子比を変えて検討し
た。結果を図２に示す。図２において横軸はＡｌ／Ｎ
（原子比）であり、縦軸はＡｌＮとして存在するＮ量を
トータルＮ量で割った値である。巻取り温度が６８０℃
の高温巻取りでは、Ａｌ／Ｎの比が小さくても、Ｎはそ
のほとんどがＡｌＮとして析出するが、５５０℃の低温
巻取りでは、ほとんどのＮをＡｌＮとして析出させるに
はＡｌ／Ｎ≧１５にする必要がある。またＡｌ量の増大
はコスト高や硬質化を招くので、その上限を０．１０重
量％とする。なおこの時原子比Ａｌ／Ｎ≧１５を満足さ
せるＮ量は０．００３６重量％以下となる。Al and N are also important constituents of the present invention. If N is not precipitated as AlN during hot rolling, fine AlN precipitates during continuous annealing and inhibits the growth of crystal grains, and as a result, the structure becomes fine grains and hardens.
On the other hand, when high-temperature winding is performed to accelerate the precipitation of AlN, the uniformity of the material such as hardness in the longitudinal direction and the width direction of the coil deteriorates as described above. So low-temperature winding with AlN
The conditions for precipitating were investigated by changing the atomic ratio of Al and N. The results are shown in Figure 2. In Fig. 2, the horizontal axis is Al / N
(Atomic ratio), and the vertical axis represents a value obtained by dividing the amount of N existing as AlN by the total amount of N. Winding temperature is 680 ℃
In the high temperature winding of Al, even if the ratio of Al / N is small, most of N is precipitated as AlN, but in the low temperature winding of 550 ° C., most of N is precipitated as AlN and Al / N ≧ 15. Need to Further, an increase in the amount of Al leads to high cost and hardening, so the upper limit is made 0.10% by weight. At this time, the amount of N satisfying the atomic ratio Al / N ≧ 15 is 0.0036% by weight or less.
【００１５】熱延後の巻取り温度を６２０℃以上にする
と巻取り後の冷却速度の違いにより、前記したようにコ
イル長手方向や幅方向においてカーバイト形態やＡｌＮ
の析出状態が均一にならず、そのため焼鈍後の材質の均
一性が悪くなる。また５５０℃未満にすると巻取り温度
制御や形状制御が困難になる。したがって熱間圧延後の
巻取り温度は５５０℃以上６２０℃未満の範囲に限定す
る。When the coiling temperature after hot rolling is set to 620 ° C. or higher, as described above, due to the difference in cooling rate after coiling, the form of carbide or AlN in the longitudinal direction or the width direction of the coil is obtained.
Does not become uniform, resulting in poor uniformity of the material after annealing. On the other hand, if the temperature is lower than 550 ° C, it becomes difficult to control the winding temperature and the shape. Therefore, the winding temperature after hot rolling is limited to the range of 550 ° C or higher and lower than 620 ° C.
【００１６】連続焼鈍の加熱温度を６５０℃未満にする
と完全には再結晶せず硬質なものしか得られない。また
前記したようにＡ1 変態点以上にするとヒートバックル
などの通板トラブルが発生する。したがって連続焼鈍時
の加熱温度を６５０℃以上Ａ 1 変態点未満の範囲に限定
する。Keep the heating temperature of continuous annealing below 650 ° C.
Therefore, it is not recrystallized completely and only a hard material is obtained. Also
As mentioned above, A1Heat buckle above the transformation point
There is a problem such as strip passing. Therefore, during continuous annealing
Heating temperature of 650 ℃ or higher A 1Limited to the range below the transformation point
To do.
【００１７】加熱後の冷却速度は、その後の過時効処理
において固溶Ｃの析出を促進するために固溶Ｃの十分な
過飽和度を確保するべく３０℃／ｓ以上に限定する。The cooling rate after heating is limited to 30 ° C./s or more in order to secure a sufficient degree of supersaturation of the solid solution C in order to promote the precipitation of the solid solution C in the subsequent overaging treatment.
【００１８】過時効処理温度を３５０℃未満にすると固
溶Ｃの析出に時間がかかり過ぎる。また４５０℃を越え
るとその温度における平衡固溶Ｃ量が多くなり冷却後の
最終製品の固溶Ｃ量も多くなる。したがって過時効処理
温度を３５０℃以上４５０℃以下の範囲に限定する。過
時効処理時間は、固溶Ｃを十分に析出させるため３０秒
以上に限定する。When the overaging treatment temperature is lower than 350 ° C., it takes too long to precipitate the solid solution C. On the other hand, when the temperature exceeds 450 ° C, the amount of equilibrium solid solution C at that temperature increases, and the amount of solid solution C of the final product after cooling also increases. Therefore, the overaging temperature is limited to the range of 350 ° C to 450 ° C. The overaging time is limited to 30 seconds or more in order to sufficiently precipitate the solid solution C.
【００１９】[0019]
【実施例】表１に示すように、本発明の主要構成要件で
あるＣ、Ａｌ、Ｎ、Ｍｎ量、熱延後の巻取り温度および
連続焼鈍時の加熱温度、冷却速度、過時効処理条件を変
えて、種々のサンプルを作成した。いずれのサンプルに
おいてもＰ、Ｓ量は０．０１０〜０．０１６重量％の範
囲内にある。表中のサンプルにおいて、実施例１〜８は
成分、製造条件いずれも本発明の範囲内にあり、特に実
施例１〜７はＣ量がより好ましい範囲内にあるサンプル
である。比較例９はＡｌ／Ｎが下限をきり、比較例９、
１０、１１は熱延後の巻取り温度が上限をきり、比較例
１２はＣ量が上限をきり、比較例１３はＣ量が下限をき
り、比較例１４、１５、１６は熱延後の巻取り温度が下
限をきり、比較例１７は連続焼鈍時の加熱温度が下限を
きり、比較例１８は連続焼鈍時の過時効処理温度が上限
をきり、比較例１９は連続焼鈍時の過時効処理時間が下
限をきり、比較例２０は連続焼鈍時の過時効処理温度が
下限をきったサンプルである。EXAMPLE As shown in Table 1, the main constituents of the present invention are C, Al, N, and Mn amounts, the coiling temperature after hot rolling, the heating temperature during continuous annealing, the cooling rate, and the overaging treatment conditions. Was changed to prepare various samples. In all the samples, the amounts of P and S are in the range of 0.010 to 0.016% by weight. In the samples in the table, Examples 1 to 8 are within the scope of the present invention in terms of both components and production conditions, and particularly Examples 1 to 7 are samples in which the C content is within a more preferable range. In Comparative Example 9, Al / N exceeds the lower limit, and Comparative Example 9,
In Nos. 10 and 11, the winding temperature after hot rolling exceeded the upper limit, in Comparative Example 12, the C amount exceeded the upper limit, in Comparative Example 13, the C amount exceeded the lower limit, and in Comparative Examples 14, 15, and 16, after the hot rolling. The winding temperature is below the lower limit, Comparative Example 17 is below the heating temperature during continuous annealing, Comparative Example 18 is above the overaging temperature during continuous annealing, and Comparative Example 19 is overaging during continuous annealing. The treatment time is below the lower limit, and Comparative Example 20 is a sample in which the overaging treatment temperature during continuous annealing is below the lower limit.
【００２０】そしてロックウェル硬度（ＨＲ３０Ｔ）と
焼付塗装をシュミレートした２１０℃×１０分の熱処理
後の降伏点伸びを測定した。またコイル長手方向および
幅方向の材質の均一性を調べるために、コイル長手方向
および幅方向に詳細にロックウェル硬度を測定し、長手
方向および幅方向の硬度差が１ポイント未満であれば
○、１ポイント以上であれば×の２段階の評価を行っ
た。Then, the Rockwell hardness (HR30T) and the yield point elongation after heat treatment simulating the baking coating at 210 ° C. for 10 minutes were measured. Further, in order to check the uniformity of the material in the coil longitudinal direction and the width direction, the Rockwell hardness is measured in detail in the coil longitudinal direction and the width direction, and if the hardness difference between the longitudinal direction and the width direction is less than 1 point, If the score is 1 point or more, a two-stage evaluation of × was performed.
【００２１】結果を表２に示す。本発明方法で作成した
実施例１〜８のサンプルは、いずれもテンパー度Ｔ３の
目標硬度５７±３を満足し、５％以下の焼付塗装処理後
の降伏点伸びを示し、材質の均一性にも優れていること
がわかる。特に実施例１〜７のサンプルは、その焼付塗
装処理後の降伏点伸びが４％以下と、フルーティングな
どの成形不良を回避する上で極めて優れている材料とい
える。一方本発明外の方法で作成したサンプルでは、比
較例９〜１１は材質の均一性が悪く、比較例９、１２〜
１３および１７〜２０は５％を越える焼付塗装処理後の
降伏点伸びを示すためフルーティングなどの成形不良の
問題を起こし、比較例１４、１５、１６、１７はＴ３の
目標硬度を越えているので、いずれもＴ３以下の加工用
軟質材としては使用できない。The results are shown in Table 2. The samples of Examples 1 to 8 prepared by the method of the present invention all satisfy the target hardness 57 ± 3 of the degree of temper T3, exhibit a yield point elongation after baking treatment of 5% or less, and show uniformity of material. Also proves to be excellent. In particular, the samples of Examples 1 to 7 have a yield point elongation of 4% or less after the baking and coating treatment, and can be said to be extremely excellent materials for avoiding molding defects such as fluting. On the other hand, in the samples prepared by the method other than the present invention, Comparative Examples 9 to 11 had poor material uniformity, and Comparative Examples 9 and 12 to
Nos. 13 and 17 to 20 show elongations at yield point after baking coating treatment of more than 5%, which causes problems of molding defects such as fluting, and Comparative Examples 14, 15, 16 and 17 exceed the target hardness of T3. Therefore, neither of them can be used as a soft material for processing having T3 or less.
【００２２】[0022]
【表１】 [Table 1]
【００２３】[0023]
【表２】 [Table 2]
【００２４】[0024]
【発明の効果】本発明は以上説明したように構成されて
いるので、低コストで、コイル長手方向や幅方向に硬度
などの材質の均一性に優れ、焼鈍時の通板トラブルも起
きず、しかも製缶などの加工時にフルーティングなどの
成形不良が起こらない連続焼鈍法によるＴ３以下の軟質
なぶりきおよびＴＦＳ用鋼板の製造方法を提供できる。EFFECTS OF THE INVENTION Since the present invention is constructed as described above, it is low in cost, excellent in the uniformity of materials such as hardness in the longitudinal direction and width direction of the coil, and there is no trouble of passing the sheet during annealing. Moreover, it is possible to provide a method for producing a soft tint of T3 or less and a steel sheet for TFS by the continuous annealing method, which does not cause molding defects such as fluting during the processing of cans and the like.
【図１】焼付塗装処理後の降伏点伸びとＣ量の関係を示
す図である。FIG. 1 is a diagram showing the relationship between yield point elongation and C content after baking coating.
【図２】熱延巻取り後のＡｌＮとして存在するＮ量をト
ータルＮ量で割った値と原子比Ａｌ／Ｎの関係を示す図
である。FIG. 2 is a diagram showing the relationship between a value obtained by dividing the amount of N existing as AlN after hot rolling and winding by the total amount of N and the atomic ratio Al / N.
Claims (2)
５、Ｍｎ：０．０５〜０．６０、Ｐ：０．０２以下、
Ｓ：０．０２以下、ＳｏｌＡｌ：０．１０以下、かつＡ
ｌとＮの原子比Ａｌ／Ｎ≧１５となるようにＮを含む鋼
を用い、熱間圧延後５５０℃以上６２０℃未満の温度域
で巻取り、次いで冷間圧延後連続焼鈍法により６５０℃
以上Ａ1 変態点未満の温度域に加熱し、その後３０℃／
ｓ以上の冷却速度で３５０℃以上４５０℃以下の温度域
まで冷却し、その温度で３０秒以上の過時効処理を行う
ことを特徴とする軟質ぶりきおよびＴＦＳ用鋼板の製造
方法。1. C: 0.050 to 0.08% by weight
5, Mn: 0.05-0.60, P: 0.02 or less,
S: 0.02 or less, SolAl: 0.10 or less, and A
Using steel containing N such that the atomic ratio of 1 and N is Al / N ≧ 15, the steel is wound in a temperature range of 550 ° C. or higher and lower than 620 ° C. after hot rolling, and then 650 ° C. by continuous annealing after cold rolling.
Heating above the temperature range below the A 1 transformation point, then 30 ° C /
A method for manufacturing a soft tin plate and a steel sheet for TFS, which comprises cooling to a temperature range of 350 ° C. or higher and 450 ° C. or lower at a cooling rate of s or higher and performing overaging treatment for 30 seconds or longer at that temperature.
であり、Ｃ以外の成分が請求項１に記載の範囲内にある
鋼を用いた請求項１に記載の軟質ぶりきおよびＴＦＳ用
鋼板の製造方法。2. C: 0.060 to 0.080 in% by weight.
The method for producing a soft tin plate and a steel sheet for TFS according to claim 1, wherein a steel having a component other than C within the range of claim 1 is used.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21290994A JP3185557B2 (en) | 1994-09-06 | 1994-09-06 | Method for manufacturing soft tinplate and soft TFS steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21290994A JP3185557B2 (en) | 1994-09-06 | 1994-09-06 | Method for manufacturing soft tinplate and soft TFS steel sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0873943A true JPH0873943A (en) | 1996-03-19 |
| JP3185557B2 JP3185557B2 (en) | 2001-07-11 |
Family
ID=16630294
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21290994A Expired - Fee Related JP3185557B2 (en) | 1994-09-06 | 1994-09-06 | Method for manufacturing soft tinplate and soft TFS steel sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3185557B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1347071A1 (en) * | 2002-03-21 | 2003-09-24 | Usinor | Cold worked aluminium killed steel sheet and process for manufacturing packaging from this metal sheet |
| JP2013185211A (en) * | 2012-03-08 | 2013-09-19 | Nippon Steel & Sumitomo Metal Corp | Surface treated steel sheet for welded can, and method for producing the same |
-
1994
- 1994-09-06 JP JP21290994A patent/JP3185557B2/en not_active Expired - Fee Related
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1347071A1 (en) * | 2002-03-21 | 2003-09-24 | Usinor | Cold worked aluminium killed steel sheet and process for manufacturing packaging from this metal sheet |
| FR2837500A1 (en) * | 2002-03-21 | 2003-09-26 | Usinor | NUT SHEET IN CALM ALUMINUM STEEL AND METHOD OF MANUFACTURING A PACKAGE FROM THIS SHEET |
| US9039846B2 (en) | 2002-03-21 | 2015-05-26 | Usinor | Cold-rolled aluminum killed steel sheet and method of manufacturing packaging from said sheet |
| JP2013185211A (en) * | 2012-03-08 | 2013-09-19 | Nippon Steel & Sumitomo Metal Corp | Surface treated steel sheet for welded can, and method for producing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3185557B2 (en) | 2001-07-11 |
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