JPH02197523A - Manufacture of steel sheet for can - Google Patents
Manufacture of steel sheet for canInfo
- Publication number
- JPH02197523A JPH02197523A JP27548889A JP27548889A JPH02197523A JP H02197523 A JPH02197523 A JP H02197523A JP 27548889 A JP27548889 A JP 27548889A JP 27548889 A JP27548889 A JP 27548889A JP H02197523 A JPH02197523 A JP H02197523A
- Authority
- JP
- Japan
- Prior art keywords
- less
- rolling
- steel
- steel sheet
- continuous annealing
- 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.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 22
- 239000010959 steel Substances 0.000 title claims abstract description 22
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 238000000137 annealing Methods 0.000 claims abstract description 33
- 238000005096 rolling process Methods 0.000 claims abstract description 26
- 239000000203 mixture Substances 0.000 claims abstract description 10
- 229910001208 Crucible steel Inorganic materials 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 238000007796 conventional method Methods 0.000 claims abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 229910052742 iron Inorganic materials 0.000 claims abstract 2
- 238000000034 method Methods 0.000 claims description 18
- 238000005097 cold rolling Methods 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 238000005098 hot rolling Methods 0.000 claims description 3
- 238000005496 tempering Methods 0.000 claims description 3
- 239000000463 material Substances 0.000 abstract description 15
- 238000007670 refining Methods 0.000 abstract description 4
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 230000003749 cleanliness Effects 0.000 abstract description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract 2
- 239000005028 tinplate Substances 0.000 description 6
- 239000007779 soft material Substances 0.000 description 5
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 4
- 238000007747 plating Methods 0.000 description 4
- 229910000655 Killed steel Inorganic materials 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000002791 soaking Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- 238000009849 vacuum degassing Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000532 Deoxidized steel Inorganic materials 0.000 description 1
- 235000013361 beverage Nutrition 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 230000001151 other effect Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 230000009897 systematic effect Effects 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、食缶や飲料缶等に使用される原板の成分組
成を限定するなどにより表面汚れを防止し、良質な原板
の得られる缶用鋼板の製造方法に関する。[Detailed Description of the Invention] [Industrial Application Field] The present invention aims at preventing surface contamination by limiting the component composition of the original plates used for food cans, beverage cans, etc., and producing cans from which high-quality original plates can be obtained. This invention relates to a method for manufacturing steel sheets for industrial use.
ぶりきの機械的性質は調質度で表示される。ＪＩＳ Ｇ
３３０３−１９７５には、−船釣なぶりきの調質度が
規定されており、製造の際の目標値としてロックウェル
Ｔ硬さ（ＨＲ−３０Ｔ）で表示され、軟質なものから硬
質なものへ順にＴ−１（４９±３）、Ｔ−２（５３±３
）、Ｔ−３（５７±３）、Ｔ−４（６１±３）、Ｔ−５
（６５±３）及びＴ−６（６９±３）に区分されている
。このうち、Ｔ−１〜Ｔ−３のいわゆる軟質板は箱焼鈍
法により、Ｔ−４〜Ｔ−６の硬質板は連続焼鈍法により
、通常製造されている。The mechanical properties of tinplate are expressed by the degree of heat treatment. JIS G
3303-1975 stipulates the degree of tempering for boat fishing, which is expressed in Rockwell T hardness (HR-30T) as a target value during manufacturing, and ranges from soft to hard. T-1 (49±3), T-2 (53±3)
), T-3 (57±3), T-4 (61±3), T-5
(65±3) and T-6 (69±3). Among these, the so-called soft plates T-1 to T-3 are usually manufactured by the box annealing method, and the hard plates T-4 to T-6 are usually manufactured by the continuous annealing method.
ところで、従来の連続焼鈍炉では急冷帯及び過時効処理
帯を有していなかったため、Ｔ−４以上の硬質板しか製
造されていなかったが、最近になって急冷帯及び過時効
処理帯を有する連続焼鈍炉が稼動するようになり、Ｔ−
３以下の軟質板を製造する技術についても、例えば、特
開昭５０−１２１１１８号等のように特許公開がなされ
ている。By the way, conventional continuous annealing furnaces did not have a quenching zone and an overaging zone, so only hard plates of T-4 or higher were manufactured. The continuous annealing furnace began to operate, and T-
Techniques for manufacturing soft plates of 3 or less have also been published as patents, such as in Japanese Patent Laid-Open No. 121118/1983.
しかし、上記のような連続焼鈍炉によれば、−般に使わ
れているＡｌキルド鋼、あるいはＡｆ含有量の少ない弱
脱酸鋼を使ってもＴ−２相当の硬さのものしか得られて
いない。従ってＴ−１相当材は依然として箱焼鈍法に拠
らざるを得なかった。However, with the above-mentioned continuous annealing furnace, even if commonly used Al-killed steel or weakly deoxidized steel with low Af content is used, only a hardness equivalent to T-2 can be obtained. Not yet. Therefore, T-1 equivalent materials still had to rely on the box annealing method.
しかしながら、箱焼鈍法には以下に述べるような種々の
問題があったことから、連続焼鈍法によるＴ−１〜Ｔ−
３材（特にＴ−１材）を製造する方法の開発が望まれて
いた。However, since the box annealing method had various problems as described below, the continuous annealing method was used for T-1 to T-
It has been desired to develop a method for manufacturing three materials (particularly T-1 material).
箱焼鈍法には、（１）タイトコイル状態で焼鈍が施され
るため、生産性の点で焼鈍温度を高くすると焼付き欠陥
（ＳｔｉｃｋｉｎｇＢｒｅａｋ）が生じて材料歩留まり
が低下する。（２）均熱には数時間以上が必要であるた
め、焼鈍中に鋼板表面の結晶粒界へＣ，Ｍｎ等が富化濃
縮され、また、Ｃをグラファイトとして析出する等の表
面汚れを生じたりし、その結果、ぶりきの耐蝕性が劣化
することがあった。（３）コイル温度は、その形状から
外巻部と内壱部は高温になり、中間部は温度が上がりに
くいため、コイル内で硬さのバラツキが大きくなり均質
な原板を得ることは困難であり、また平坦度も悪化して
いた。以上のように、箱焼鈍法では良質なＴ−１〜Ｔ−
３級の軟質ぶりき原板の製造は困難であった。In the box annealing method, (1) since annealing is performed in a tight coil state, if the annealing temperature is increased from the viewpoint of productivity, sticking defects will occur and the material yield will decrease. (2) Because soaking requires several hours or more, C, Mn, etc. are enriched and concentrated in the grain boundaries of the steel sheet surface during annealing, and surface stains such as C precipitated as graphite occur. As a result, the corrosion resistance of tinplate may deteriorate. (3) Due to its shape, the coil temperature is high at the outer winding part and the inner part, and it is difficult to raise the temperature at the middle part, so there is a large variation in hardness within the coil, making it difficult to obtain a homogeneous original sheet. Moreover, the flatness was also deteriorating. As mentioned above, the box annealing method produces high quality T-1 to T-
It was difficult to manufacture grade 3 soft tin plate.
この発明は、このような従来の問題にかんがみてなされ
たものであって、原板の成分組成を限定するとともに、
連続焼鈍後に調質圧延を施すことにより上記課題を解決
することを目的としている。This invention was made in view of such conventional problems, and as well as limiting the component composition of the original plate,
The purpose is to solve the above problems by performing skin pass rolling after continuous annealing.
この発明は、組成が重量比で、Ｃ： ０． ＯＯ４％以
下、Ｓｔ：０．０４％以下、 Ｍｎ ： ０．０５〜０
．３％、Ｓ：０．０２％以下、Ｐ：０．０２％以下、Ａ
ｌ： ０．０２〜０．１５％、Ｎ：０．００４％以下、
Ｎｂ： ０．０１％以下を含有し、残部は実質的にＦｅ
よりなる連続鋳造鋼片を用い、常法で熱間圧延、酸洗、
冷間圧延を施してから連続焼鈍を施してロックウェル硬
度（ＨＲ−３０Ｔ）で４９±３にした後、引続き施され
る調質圧延の圧延率を変化させて所望の調質度を有する
缶用鋼板を得ることを特徴とする缶用鋼板の製造方法と
したものである。This invention has a composition in weight ratio of C: 0. OO4% or less, St: 0.04% or less, Mn: 0.05-0
．． 3%, S: 0.02% or less, P: 0.02% or less, A
L: 0.02 to 0.15%, N: 0.004% or less,
Nb: Contains 0.01% or less, the remainder is substantially Fe
Using continuous cast steel slabs, hot rolling, pickling, and
After performing cold rolling and continuous annealing to obtain a Rockwell hardness (HR-30T) of 49±3, a can having a desired temper degree is obtained by changing the rolling rate of subsequent temper rolling. This is a method for manufacturing a steel plate for cans, which is characterized by obtaining a steel plate for cans.
この発明は、上記のような構成としたので、箱焼鈍法に
よる際に生じた前記不具合を回避することができる。す
なわち、連続焼鈍法によるため板の温度のバラツキや焼
付きを生じず、材料歩留りは向上し、また成分組成を限
定したことと相俟って表面汚れは生じない。更に、調質
圧延における圧延率を変えることにより、Ｔ−１〜Ｔ−
３の軟質材ばかりでなく、Ｔ−４以上の硬質材も得るこ
とができる。Since the present invention has the above-described configuration, it is possible to avoid the problems described above that occur when using the box annealing method. That is, since the continuous annealing method is used, there is no variation in the temperature of the plate or seizure, the material yield is improved, and together with the limited component composition, no surface stains occur. Furthermore, by changing the rolling rate in temper rolling, T-1 to T-
Not only the soft material of T-3 but also the hard material of T-4 or higher can be obtained.
以下、本発明に到る過程、及び成分組成の限定理由につ
いて述べる。The process leading to the present invention and the reason for limiting the component composition will be described below.
本発明者らは、製鋼時に真空脱ガス処理を有効に駆使し
て、（Ｊｌを極微量にした／ｌキルド鋼スラブを使用す
ることにより、連続焼鈍法によっても調質度Ｔ−１の原
板を製造できること、ならびに上記Ａｆキルド鋼中に炭
化物形成元素であるＮｂを含有させたものを使用するこ
とにより従来の箱焼鈍法で得られていたものと同等以上
の機械的性質を有する原板を製造することが可能である
ことに着目して本発明を完成した。The present inventors have effectively utilized vacuum degassing treatment during steel manufacturing, and by using (/l) killed steel slabs with an extremely small amount of Jl, the original plate with a refining degree of T-1 can be obtained even by continuous annealing. By using the above-mentioned Af killed steel containing Nb, which is a carbide-forming element, we can manufacture original sheets with mechanical properties equivalent to or better than those obtained by conventional box annealing. The present invention was completed by focusing on the fact that it is possible to do this.
即ち、本発明者らは、ぶりきの硬さに及ぼす固溶Ｃ，Ｎ
及び結晶粒径との関係を系統的に調べた結果、固溶Ｃ２
Ｎが少なく且つ結晶粒径が大きくなると軟質になること
を知見し、この知見に基づいて焼鈍後に固溶Ｃを少なく
するため、出発材である連鋳鋼片製造用溶鋼中のＣを極
端に少なくすれば良いと考えられ、またＮはＡｌＮとし
て析出させれば軟質になる。以上の観点から、同一の素
材を使用し、連続焼鈍でＴ−１相当以下の軟質材を得て
、この軟質材に圧延率をそれぞれ変えて調質圧延するこ
とによりＴ−１〜Ｔ−６の原板にそれぞれ作り分ける知
見をさらに得たものである。That is, the present inventors have discovered that solid solution C and N have an effect on the hardness of tinplate.
As a result of a systematic investigation of the relationship between solid solution C2 and crystal grain size,
We discovered that the less N and the larger the grain size, the softer the material becomes.Based on this knowledge, in order to reduce the amount of solid solute C after annealing, we drastically reduced the amount of C in the starting material, molten steel for continuous cast billet production. It is thought that it is sufficient to do this, and if N is precipitated as AlN, it becomes soft. From the above viewpoint, by using the same raw material, obtaining a soft material equivalent to T-1 or less by continuous annealing, and applying temper rolling to this soft material at different rolling rates, T-1 to T-6 We have gained further knowledge on how to make different original plates.
次に成分組成を限定する理由について説明する。Next, the reason for limiting the component composition will be explained.
Ｃは、第１図に示すようにＣ量が０．００４％以下の極
微量となると軟質化し、逆にＣ量が増加すると約０．０
１％において最も硬さが高くなる。従って連続焼鈍炉に
より調質度Ｔ−１相当材を製造するためには、Ｃは０．
００４％以下にする必要がある。As shown in Figure 1, C becomes soft when the amount of C becomes extremely small, below 0.004%, and conversely, when the amount of C increases, it softens to about 0.04%.
Hardness is highest at 1%. Therefore, in order to produce a material with a refining degree of T-1 using a continuous annealing furnace, C must be 0.
It is necessary to keep it below 0.004%.
Ｓｉは、ぶりきの耐蝕性を劣化させるほか、さらに材質
を極端に硬化させる元素であるので、Ｓｉを過剰に含有
させることは避けるべきである。Si is an element that not only deteriorates the corrosion resistance of tinplate but also extremely hardens the material, so it should be avoided to contain Si in excess.
従ってＳｉは０．０４％以下にする必要がある。Therefore, Si needs to be 0.04% or less.
Ｍｎは、熱延コイルの耳割れ発生を防止するために添加
するものであるが、０．０５％より少ないと耳割れの発
生を防止することができず、また０゜３％より多いと硬
質化するので、Ｍｎの含有範囲は０．０５〜０．３％で
ある必要がある。Mn is added to prevent the occurrence of edge cracks in hot rolled coils, but if it is less than 0.05%, it will not be possible to prevent the occurrence of edge cracks, and if it is more than 0.3%, it will cause hardness. Therefore, the content range of Mn needs to be 0.05 to 0.3%.
また、ＳはＭｎ量との関係において過剰に含有すると熱
延コイルの耳割れを発生させるとともにＳ系介在物をな
してプレス欠陥となるので、Ｓは０．０２％以下にする
必要がある。Furthermore, in relation to the amount of Mn, if S is contained in excess, it will cause edge cracks in the hot-rolled coil and form S-based inclusions, resulting in press defects, so S needs to be kept at 0.02% or less.
Ｐは、材質を硬化させ且つぶりきの耐蝕性を劣化させる
元素なので過剰の含有は好ましくなく、０．０２％以下
にする必要がある。Since P is an element that hardens the material and deteriorates the corrosion resistance of the material, it is not preferable to contain it in excess, and it is necessary to keep it at 0.02% or less.
Ａ２は、その過剰添加は経済的にも好ましくないので、
０．１５％以下とし且つ下限は０．０２％より少ないと
鋼中の固溶Ｎ量がＡｆＮとならない分だけ残存するので
、Ａｌは０．０２％以上とする必要があり、従ってＡｆ
は０．０２〜０．１５％の範囲に限定する。Since excessive addition of A2 is economically undesirable,
If it is 0.15% or less and the lower limit is less than 0.02%, the amount of solid solute N in the steel that does not become AfN will remain, so Al needs to be 0.02% or more, and therefore, Af
is limited to a range of 0.02 to 0.15%.
Ｎは、鋼中に固溶していると軟質な鋼板が得られにくく
なるので、上記Ａｌとの関係上、０．００４％以下にす
る必要がある。If N is dissolved in steel, it will be difficult to obtain a soft steel plate, so it needs to be kept at 0.004% or less in relation to the above-mentioned Al.
Ｎｂは、炭化物形成元素であって、固溶Ｃの残存を少な
くする機能を有するが、多量な添加は製造コストを上昇
することになるので必要最低限とすることが望ましい。Nb is a carbide-forming element and has the function of reducing the residual solid solution C, but since adding a large amount increases manufacturing costs, it is desirable to keep it to the minimum necessary amount.
従ってＮｂは０．０１％以下にする必要がある。Therefore, Nb needs to be 0.01% or less.
上記のごとく連続鋳造鋼片を用い、常法で熱間圧延、酸
洗、冷間圧延を施し、ロックウェル硬さ（ＨＲ−３０Ｔ
）で５０以下にした後、調質圧延の圧延率で調質度Ｔ−
１−Ｔ−６に作り分けることを特徴としている。第２図
は連続焼鈍後、Ｔ−１相当の軟質材を用いて調質圧延に
よる加工硬化を利用してＴ−１〜Ｔ−６の原板に作り分
けることができることを示した線図である。Using the above-mentioned continuous cast steel billets, hot rolling, pickling, and cold rolling were carried out in the usual manner to achieve Rockwell hardness (HR-30T).
) to 50 or less, and then the temper degree T- with the rolling rate of temper rolling.
It is characterized by being divided into 1-T-6. Fig. 2 is a diagram showing that after continuous annealing, it is possible to use a soft material equivalent to T-1 to create original sheets of T-1 to T-6 using work hardening by temper rolling. .
なお、本発明の鋼板では硬度に及ぼす連続焼鈍時の均熱
時間の影響は小さ（、コストの点から均熱時間は短い方
が好ましい。In addition, in the steel sheet of the present invention, the influence of the soaking time during continuous annealing on the hardness is small (although from the viewpoint of cost, the shorter the soaking time is, the better.
以下、本発明の実施例を第１表及び第１． ２図を参照
して説明する。Examples of the present invention are shown in Table 1 and Table 1 below. This will be explained with reference to FIG.
先ず鋼を底吹き転炉により溶製し、Ｃ： ０．０３％と
して出鋼した。続いてＲ−Ｈ真空脱ガス装置を用いて脱
炭処理を施した後、／ｌ、Ｎｂを添加して第１表に示す
ような成分組成とした。これらを連続鋳造機で鋼片とな
し、この鋼片を熱間圧延温度８６０°Ｃ１熱間巻取り温
度６２０°Ｃでそれぞれ２．８ｆｆＩ［ｌｌ厚の圧延コ
イルとした後、酸洗により脱スケールした。次に６スタ
ンドタンデム冷間圧延機により０．３ ａｍの板厚に圧
延した後、第１表に示すヒートサイクルで連続焼鈍を施
した。次いで実験例番号１〜３および１１〜１４は調質
圧延機にて圧延率１％で、実験例番号４〜９については
焼鈍までは同一条件で行ったものを圧延率のみを１゜３
．５，１０，２０．３０％の６水準となし、加工硬化に
よる高調質度を求めた。また、実験例番号１０は箱焼鈍
法によるものである。First, steel was melted in a bottom blowing converter and tapped with a C content of 0.03%. Subsequently, after decarburizing using an R-H vacuum degassing device, Nb was added to give the composition as shown in Table 1. These are made into steel slabs using a continuous casting machine, and these steel slabs are hot rolled at a temperature of 860°C and hot coiled at a temperature of 620°C to form rolled coils with a thickness of 2.8ffI [ll], and then descaled by pickling. did. Next, after rolling to a thickness of 0.3 am using a 6-stand tandem cold rolling mill, continuous annealing was performed using the heat cycle shown in Table 1. Next, Experimental Example Nos. 1 to 3 and 11 to 14 were carried out using a temper rolling mill at a rolling rate of 1%, and Experimental Examples Nos. 4 to 9 were carried out under the same conditions up to annealing, but only at a rolling rate of 1°3.
．． Six levels of 5, 10, and 20.30% were used to determine the high degree of tempering due to work hardening. Further, Experimental Example No. 10 is based on the box annealing method.
調質圧延を施した後、ハロゲンタイプの電気スズめっき
ラインにて＃２５ （２，８８／ｎ’ｒ＞のスズめっき
およびリフロー処理（溶鍋化処理）を連続して施し、光
沢のあるぶりきに仕上げた。これらのぶりきから供試材
を採取して硬さ（ＨＲ−３０Ｔ）を測定し、さらに乾湿
繰返し試験にて耐錆性評価を行った。耐錆性試験では錆
の発生しなかったものを良（Ｏ印で表示）、錆の発生し
たもの（×印で表示）で判定した。After temper rolling, #25 (2,88/n'r) tin plating and reflow treatment (molten pot processing) are continuously performed on a halogen-type electrolytic tin plating line to create a shiny tin plate. The hardness (HR-30T) was measured by collecting test materials from these tinplates, and the rust resistance was evaluated using dry and wet repeated tests. Those with no rust were judged as good (indicated by an O mark), and those with rust (indicated by an X mark).
第１表より明らかなように、連続焼鈍法でも軟質原板は
得られているし、調質圧延率をより高くすることにより
Ｔ−２，Ｔ−３，Ｔ−４，Ｔ−５゜Ｔ−６と作り分ける
こともできる。又、耐錆性試験も良好であった。As is clear from Table 1, soft original sheets can be obtained even with the continuous annealing method, and by increasing the temper rolling rate, T-2, T-3, T-4, T-5゜T- It can also be made into 6. Moreover, the rust resistance test was also good.
以上説明したように本発明によれば、従来のように箱焼
鈍によらず連続焼鈍により軟質材Ｔ−１〜Ｔ−３が得ら
れ、さらに調質圧延の圧延率の変化によりＴ−１−Ｔ−
６に至る、軟質、硬質材が作り分けられるので、箱焼鈍
法による欠点を解消するとともに、素材の統合が可能で
生産性、経済性とも大幅に向上改善できる。なお、調質
圧延の圧下率をさらに高くすることによりＤＲ−８，Ｄ
Ｒ−９，ＤＲ−１０も得られる。さらに本発明によるこ
れらの鋼板は表面汚れが生ぜず、表面清浄性に優れてい
るのでＺｎめっき、Ｎｉめっき等、広く表面処理用鋼板
として使用できる等、多くの効果が得られる。As explained above, according to the present invention, soft materials T-1 to T-3 can be obtained by continuous annealing instead of box annealing as in the conventional method, and T-1-T-3 can be obtained by changing the rolling ratio of temper rolling. T-
6, soft and hard materials can be made separately, which eliminates the disadvantages of the box annealing method, and also enables the integration of materials, greatly improving both productivity and economy. In addition, by further increasing the rolling reduction of skin pass rolling, DR-8, D
R-9 and DR-10 are also obtained. Further, these steel sheets according to the present invention do not cause surface stains and have excellent surface cleanliness, so that they can be used as steel sheets for a wide range of surface treatments such as Zn plating, Ni plating, etc., and many other effects can be obtained.
第１図は、鋼板のＣ含有量（ｗｔ％）と硬さ（ＨＲ−３
０７）との関係を示す線図、第２図は調質圧延の圧延率
（％）と硬さ（ＨＲ−３０７）との関係を示す線図であ
る。Figure 1 shows the C content (wt%) and hardness (HR-3
07), and FIG. 2 is a diagram showing the relationship between the rolling ratio (%) of temper rolling and hardness (HR-307).
Claims (1)
０．０４％以下、Ｍｎ：０．０５〜０．３％、Ｓ：０．
０２％以下、Ｐ：０．０２％以下、Ａｌ：０．０２〜０
．１５％、Ｎ：０．００４％以下、Ｎｂ：０．０１％以
下を含有し、残部は実質的にＦｅよりなる連続鋳造鋼片
を用い、常法で熱間圧延、酸洗、冷間圧延を施してから
連続焼鈍を施してロックウェル硬度（ＨＲ−３０Ｔ）で
４９±３にした後、引続き施される調質圧延の圧延率を
変化させて所望の調質度を有する缶用鋼板を得ることを
特徴とする缶用鋼板の製造方法。(1) Composition by weight: C: 0.004% or less, Si:
0.04% or less, Mn: 0.05-0.3%, S: 0.
02% or less, P: 0.02% or less, Al: 0.02-0
．． Using a continuously cast steel billet containing 15%, N: 0.004% or less, Nb: 0.01% or less, and the remainder substantially consisting of Fe, hot rolling, pickling, and cold rolling were carried out by conventional methods. After applying continuous annealing to achieve a Rockwell hardness (HR-30T) of 49±3, the rolling rate of the subsequent temper rolling is changed to produce a steel plate for cans having a desired degree of tempering. A method for manufacturing a steel plate for cans, characterized in that:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27548889A JPH02197523A (en) | 1988-10-28 | 1989-10-23 | Manufacture of steel sheet for can |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27208188 | 1988-10-28 | ||
| JP63-272081 | 1988-10-28 | ||
| JP27548889A JPH02197523A (en) | 1988-10-28 | 1989-10-23 | Manufacture of steel sheet for can |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02197523A true JPH02197523A (en) | 1990-08-06 |
Family
ID=26550019
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27548889A Pending JPH02197523A (en) | 1988-10-28 | 1989-10-23 | Manufacture of steel sheet for can |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02197523A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5587027A (en) * | 1994-02-17 | 1996-12-24 | Kawasaki Steel Corporation | Method of manufacturing canning steel sheet with non-aging property and superior workability |
| JP2013119649A (en) * | 2011-12-07 | 2013-06-17 | Jfe Steel Corp | Original plate for steel sheet for can, steel sheet for can, and method for producing them |
| JP2016130361A (en) * | 2015-01-09 | 2016-07-21 | Ｊｆｅスチール株式会社 | Steel sheet for can and method for manufacturing steel sheet for can |
-
1989
- 1989-10-23 JP JP27548889A patent/JPH02197523A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5587027A (en) * | 1994-02-17 | 1996-12-24 | Kawasaki Steel Corporation | Method of manufacturing canning steel sheet with non-aging property and superior workability |
| JP2013119649A (en) * | 2011-12-07 | 2013-06-17 | Jfe Steel Corp | Original plate for steel sheet for can, steel sheet for can, and method for producing them |
| JP2016130361A (en) * | 2015-01-09 | 2016-07-21 | Ｊｆｅスチール株式会社 | Steel sheet for can and method for manufacturing steel sheet for can |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPS59140333A (en) | Manufacture of cold rolled steel sheet for deep drawing with superior secondary workability and surface treatability | |
| JPS5827933A (en) | Production of t-3 mild blackplate having excellent corrosion resistance by continuous annealing | |
| CN107177788A (en) | A kind of secondary cold-rolling tin plate and its production method | |
| JPH0152450B2 (en) | ||
| JPH02197523A (en) | Manufacture of steel sheet for can | |
| JPS5938338A (en) | Production of ultra thin steel sheet having high yield strength and drawability | |
| JPH0341529B2 (en) | ||
| JPS62161919A (en) | Manufacture of hard sheet steel for can excellent in drawability and minimized in anisotropy | |
| JPH02118024A (en) | Manufacture of steel sheet for can | |
| JP2004204252A (en) | Ti-CONTAINING HIGH-WORKABILITY FERRITIC CHROMIUM STEEL SHEET SUPERIOR IN RIDGING RESISTANCE, AND MANUFACTURING METHOD THEREFOR | |
| JPS6114216B2 (en) | ||
| JPH0317892B2 (en) | ||
| JPS6330969B2 (en) | ||
| JPS5857490B2 (en) | Manufacturing method of cold rolled steel sheet for deep drawing | |
| JPS6237094B2 (en) | ||
| JPS60110845A (en) | Cold rolled steel sheet for enamel and its manufacture | |
| JPH02118026A (en) | Manufacture of steel sheet for can | |
| KR100334580B1 (en) | A method of manufacturing high strength black plate having uniform hardeness and no earing | |
| JPH02141535A (en) | Production of steel sheet for drawn can decreased earing | |
| JP3273383B2 (en) | Cold rolled steel sheet excellent in deep drawability and method for producing the same | |
| JPH08143969A (en) | Production of cold rolled steel sheet excellent in workability | |
| JP2980486B2 (en) | Manufacturing method of steel plate for non-aging low earring container | |
| JP4283574B2 (en) | Steel plate for high age-hardening containers with excellent canability and method for producing the same | |
| KR910003878B1 (en) | Making process for black plate | |
| JP2980488B2 (en) | Method for producing steel sheet for low earring container |