JPH02118024A - Manufacture of steel sheet for can - Google Patents
Manufacture of steel sheet for canInfo
- Publication number
- JPH02118024A JPH02118024A JP27208388A JP27208388A JPH02118024A JP H02118024 A JPH02118024 A JP H02118024A JP 27208388 A JP27208388 A JP 27208388A JP 27208388 A JP27208388 A JP 27208388A JP H02118024 A JPH02118024 A JP H02118024A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- less
- hardness
- steel
- rolling
- 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 27
- 239000010959 steel Substances 0.000 title claims abstract description 27
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 12
- 238000000137 annealing Methods 0.000 claims abstract description 30
- 238000005096 rolling process Methods 0.000 claims abstract description 23
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 238000005097 cold rolling Methods 0.000 claims description 4
- 229910001208 Crucible steel Inorganic materials 0.000 claims description 3
- 238000005098 hot rolling Methods 0.000 claims description 3
- 238000005554 pickling Methods 0.000 claims description 3
- 238000005496 tempering Methods 0.000 claims description 3
- 238000000034 method Methods 0.000 abstract description 16
- 239000000203 mixture Substances 0.000 abstract description 8
- 229910052799 carbon Inorganic materials 0.000 abstract description 5
- 230000003749 cleanliness Effects 0.000 abstract description 5
- 238000007670 refining Methods 0.000 abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 3
- 239000010960 cold rolled steel Substances 0.000 abstract 2
- 239000006185 dispersion Substances 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000000463 material Substances 0.000 description 11
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 5
- 239000005028 tinplate Substances 0.000 description 5
- 238000007747 plating Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000007787 solid Substances 0.000 description 3
- 229910000655 Killed steel Inorganic materials 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000001953 recrystallisation 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
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 229910052736 halogen Inorganic materials 0.000 description 1
- 150000002367 halogens Chemical class 0.000 description 1
- 230000001151 other effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000007779 soft material Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000005029 tin-free steel Substances 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
- 239000002023 wood Substances 0.000 description 1
Landscapes
- 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、食缶や飲料缶に使用されるふりき。[Detailed description of the invention] [Industrial application field] This invention is a furiki used for food cans and beverage cans.
ティンフリースチール（ＴＦＳ）及び１錫めっきぶりき
（ＬＴＳ）等用の原板について、その表面清浄性を改善
することによって上記用途での適合性を図った缶用鋼板
の製造方法に関する。The present invention relates to a method for producing steel sheets for cans, which improves the surface cleanliness of original sheets for tin-free steel (TFS), tin-plated tin (LTS), etc., to achieve suitability for the above-mentioned uses.
ぶりきの機械的性質は調質度で表示される。ＪＴＳ 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
硬さ（ＨＲ−３０７）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
。The mechanical properties of tinplate are expressed by the degree of heat treatment. JTSG
3303-1975 stipulates the degree of tempering for boat fishing, which is expressed in Rockwell hardness (HR-307) as a target value during manufacturing, and changes from soft to hard. T-1 (49±3), T-2 (53±3) in order
, T-3 (57±3), T-4-(61±3), T-5
(65±3) and T-6 (69±3).
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。Among these, the so-called soft plates of T-1 to T-3 are made by the box annealing method, and the hard plates of T-4 to T=6 are made by the continuous annealing method.
Usually manufactured.
ところで、従来の連続焼鈍炉では２、冷帯及び過時効処
理帯を備えていないため、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
理帯を備えた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特許公開がなさ
れている。By the way, conventional continuous annealing furnaces are not equipped with a cooling zone or an over-aging zone, so only hard plates of T-4 or higher have been manufactured. The equipped continuous annealing furnace began to operate, and T-3
Patents have also been published regarding the following technology for manufacturing soft plates.
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Ａ２キルド鋼、あるいはＡ２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 A2 killed steel or weakly deoxidized steel with a low A2 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-
There was a desire to develop a method for manufacturing the three materials.
すなわち、箱焼鈍法には、下記（１）〜（３）に示すよ
うな欠点のあることが知られていた。（１）タイトコイ
ル状態で焼鈍が施されるために、焼鈍温度を高くすると
焼付き欠陥（Ｓｔｉｃｋｉｎｇ Ｂｒｅａｋ）が生じて
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のＣ，Ｍｎ
等が富化ｍｋ’？ｉ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て、その結果ぶり
きの耐蝕性が劣化することがあった。That is, it has been known that the box annealing method has the following drawbacks (1) to (3). (1) Since annealing is performed in a tight coil state, when the annealing temperature is increased, sticking defects occur and the yield decreases. (2) Because soaking requires several hours or more, C and Mn are absorbed into the grain boundaries on the surface of the steel sheet during annealing.
etc. are enriched mk'? In addition, surface stains such as precipitation of C as graphite may occur, resulting in deterioration of the corrosion resistance of tinplate.
（３）コイル温度は、その形状から外巻部と内巻部は高
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って均質な原板を得ること
は困難であり、その結果、平坦度も劣化していた。(3) Due to its shape, the coil temperature is high at the outer and inner winding parts, and it is difficult to raise the temperature at the middle part, which increases the variation in hardness within the coil, making it difficult to obtain a homogeneous original plate. As a result, the flatness was also deteriorated.
以上のように箱焼鈍法では良質なＴ−１〜Ｔ−３級の軟
質ふりき原板の製造は困難であった。As described above, it is difficult to produce high-quality soft sheet metal sheets of T-1 to T-3 grade using the box annealing method.
この発明は、このような従来の問題点にかんがみてなさ
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 these conventional problems, and aims to solve the above problems by limiting the composition of the original sheet and performing skin pass rolling after continuous annealing. There is.
〔課題を解決するための手段］ この発明は、重量比で、Ｃ： ０．００４％以下。[Means to solve the problem] In this invention, C: 0.004% or less in weight ratio.
Ｓｉ：０．０４％以下、 Ｍｎ ： ０．０５〜０．３
％。Si: 0.04% or less, Mn: 0.05 to 0.3
%.
Ｓ ： ０．０２％以下、Ｐ：０．０２％以下、ＡＸ：
Ｏ。S: 0.02% or less, P: 0.02% or less, AX:
O.
０２〜０．１５％、Ｎ：０．００４％以下の成分を含有
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５０以下
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
るものである。Using a continuously cast steel billet containing 02 to 0.15%, N: 0.004% or less, and the remainder substantially consisting of Fe,
After hot rolling, pickling, and cold rolling in a conventional manner, continuous annealing is performed to reduce the Rockwell hardness (HR-30T) to 50 or less, and the rolling rate of the subsequent temper rolling is changed. The present invention is characterized in that a steel sheet for cans having a desired degree of tempering is obtained.
この発明は上記のような構成としたので、箱焼鈍法によ
る際に生じた前記欠点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
を発生させず、材料歩留まりは向上し、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 structure, it is possible to avoid the drawbacks that occur when using the box annealing method. That is, since the continuous annealing method is used, variations in the temperature of the plate and seizure do not occur, 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、及び成分組成の限度理由につ
き述べる。Hereinafter, the process leading to the present invention and the reasons for limitations on component composition will be described.
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、ｃｌを極微量にしたＡＩ！、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 effectively utilized vacuum degassing treatment during steel manufacturing to reduce the amount of Cl to an extremely small amount in AI! By using a killed steel slab, it is possible to produce a master plate with a heat treatment degree of T-1 even by continuous annealing, which makes it possible to produce a master plate with mechanical properties equivalent to or better than those obtained by the conventional box annealing method. The present invention was completed by focusing on the fact that it can be manufactured.
即ち本発明者らは、ふ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ｃ、Ｎ
が少な（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９９ 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よく、またＮはＡＩＮとして析出さ
せれば軟質になると推測した。以上の観点から、同一の
素材を使用し、連続焼鈍でＴ−１相当にまで軟質な原板
を製造して、この原板に調質圧延の圧延率を変えること
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 systematically investigated the relationship between solid solute C, N and crystal grain size on the hardness of furiki, and found that solid solute C, N
Based on this knowledge, in order to reduce the amount of hard 99C after annealing, the C content in the molten steel for continuous cast billet production, which is the starting material, was extremely reduced. We also assumed that if N was precipitated as AIN, it would become soft.From the above point of view, using the same material, we manufactured a soft original plate equivalent to T-1 by continuous annealing, and this original plate We have further obtained the knowledge that T-1 to T-6 original plates can be produced separately by changing the rolling rate of temper rolling.
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、ｃｌがＯ，ＯＯ４％以下の
極微量となると軟質化し、一方、ｃｌが増加すると約０
．０１％において最も硬さが高（なる。As shown in Fig. 1, C becomes soft when Cl becomes an extremely small amount of 4% or less of O, OO, and on the other hand, as Cl increases, it becomes approximately 0.
．． The hardness is the highest at 01%.
従って連続焼鈍炉により調質度Ｔ−３以下の軟質ぶりき
原板を製造するためには、Ｃは０．００４％以下にする
必要がある。Therefore, in order to produce a soft tin plate with a refining degree of T-3 or less using a continuous annealing furnace, the C content must be 0.004% or less.
Ｓｉは、ぶりきの耐蝕性を劣化させるほか、さらに材質
を極端に硬質化する元素であるので、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 makes the material extremely hard, 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
することが必要であるが、０．０５％より少ないと耳割
れ発生を防止できず、一方、０．３％より多いと硬質化
するので、その含有範囲は０．０５〜０．３％である必
要がある。It is necessary to add Mn to prevent edge cracking in hot rolled coils, but if it is less than 0.05%, edge cracking cannot be prevented, while if it is more than 0.3%, it becomes hard. Therefore, the content range needs to be 0.05 to 0.3%.
Ｓは、Ｍｎ量との関係において過剰に含有すると熱延コ
イルの耳割れを生じさせ、またＳ系介在物となってプレ
ス欠陥を生じるので、Ｓは０．０２％以下とする必要が
ある。If S is contained excessively in relation to the Mn content, it will cause edge cracks in the hot-rolled coil, and it will also become S-based inclusions that will cause press defects, so S needs to be 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、Ｐは０．０２
％以下にする必要がある。P is an element that hardens the material and deteriorates the corrosion resistance of the wood, so it is undesirable to contain it in excess, and P is 0.02
% or less.
Ａｌは、過剰の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Ｎｉｔが／ＩＮ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Ａ
ｌは０，０２〜０．１５％の範囲に限定する。Since excessive addition of Al is economically unfavorable, the addition of Al is 0.
．． If the lower limit is 15% or less, and the lower limit is less than 0.02%, the amount of solid solute Ni in the steel that does not become /IN will remain, so Al needs to be 0.02% or more, and therefore A
l 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
なる不必要な元素であるが、製鋼時に溶鋼中に空気が混
入することにより増加する。従って空気混入防止を図れ
ば少ない量で仕上げることができる。しかしそれを実施
すると製造原価が大きくなり好ましくない。そこで採算
上の範囲で材質を維持できる量として、Ｎは０．００４
％以下にする必要がある。N is an unnecessary element that makes it difficult to obtain a soft steel plate if it is dissolved in steel, but it increases when air is mixed into molten steel during steel manufacturing. Therefore, if you try to prevent air from entering, you can finish the product with a smaller amount. However, if this is done, the manufacturing cost will increase, which is not preferable. Therefore, N is 0.004 as the amount that can maintain the material quality within a profitable range.
% or less.
上記のごとく連続鋳造鋼片を用いて、常法で熱間圧延、
酸洗、冷間圧延を行った後、連続焼鈍をは施すに際し、
第３図に示すように極低炭素鋼としては低温で焼鈍を行
う。一般に極低炭素鋼を使うに際し、Ｎｂを添加した鋼
板が用いられるが、第３図に示すように再結晶温度が高
温となり、特に缶用鋼板のように極薄材ではＣＡＬ通板
コストが大きくなる。本発明の目的の一つには経済性が
あり、ＣＡＬを低温度で通板できることは重要な条件の
一つとなる。従って組成中にＮｂを含まないことが望ま
しい。As mentioned above, using continuous cast steel billet, hot rolling by conventional method,
After pickling and cold rolling, when performing continuous annealing,
As shown in FIG. 3, ultra-low carbon steel is annealed at a low temperature. Generally, when using ultra-low carbon steel, Nb-added steel sheets are used, but as shown in Figure 3, the recrystallization temperature is high, and the CAL threading cost is high, especially for ultra-thin materials such as steel sheets for cans. Become. One of the objectives of the present invention is economic efficiency, and being able to pass CAL at low temperature is one of the important conditions. Therefore, it is desirable that the composition does not contain Nb.
よって、上記連続焼鈍を施し、ロックウェル硬さ（ＨＲ
−３０７）で５０以下とした後、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本発明は特徴と
している。Therefore, the above-mentioned continuous annealing was performed and the Rockwell hardness (HR
-307) to 50 or less, the present invention is characterized in that the temper degree is divided into T-1 to T-6 by the rolling reduction of temper rolling.
以下、この発明の実施例を第１表及び第１図〜第３図を
参照して説明する。先ず鋼を２７０を底吹き転炉により
溶製し、Ｃ： ０．０３％となして出鋼した。続いてＲ
−Ｈ真空脱ガス処理を施した後、Ａ１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’Ｃ，熱間巻
取り温度６２０°Ｃでそれぞれ２．８ ｍｍ厚の熱延コ
イルとなした後、酸洗により脱スケールした０次に６ス
タンドタンデム冷間圧延機にて０．３ ｔｍの板厚に圧
延した後、第１表に示す熱サイクルで連続焼鈍を施した
。続いて調質圧延機にて圧延率１％及び実施例５〜９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１．３，５．１５％の４水準となし、加工硬化によ
る高１１質度を求めた。Examples of the present invention will be described below with reference to Table 1 and FIGS. 1 to 3. First, 270 steel was melted in a bottom blowing converter, and the steel was tapped with a C content of 0.03%. followed by R
After performing the -H vacuum degassing treatment, A1 was added to obtain a component composition as shown in Table 1. These were made into steel slabs using a continuous casting machine, and these steel slabs were hot-rolled at a temperature of 860'C and hot-rolled at 620°C to form hot-rolled coils with a thickness of 2.8 mm, respectively, and then pickled. After rolling to a thickness of 0.3 tm using a descaled 0-order 6-stand tandem cold rolling mill, continuous annealing was performed using the heat cycle shown in Table 1. Next, in a temper rolling mill, the rolling rate was 1%, and Examples 5 to 9 were performed under the same conditions up to annealing, but only the rolling rate was changed to 4 levels of 1.3 and 5.15%, and processed. The high 11 quality due to hardening was determined.
ｉＡ質圧延を施した後、ハロゲンタイプの電気錫めっき
工程にて＃ ２５ （２，８ｇ ／ ｎＯの錫めっき及
びリフロー処理（溶湯化処理）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
採取してロックウェル硬さ（ＨＲ−３０７）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 IA quality rolling, #25 (2.8 g/nO tin plating and reflow treatment (molten metal treatment) were continuously applied using a halogen type electro-tin plating process, resulting in a glossy tin plate. Sample materials were collected from these tinplates and their Rockwell hardness (HR-307) was measured.
Furthermore, rust resistance was evaluated using dry and wet repeated tests. In the rust resistance test, those with no rust were rated as good (indicated by an O mark).
Judgment was made based on the appearance of 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、連続焼鈍で
は製造が不可能であるといわれていた調質度Ｔ−１〜Ｔ
−３級のいわゆる軟質ふりき原板をＣＡＬで製造できる
結果、表面清浄性に（Ｚれ、硬さのバラツキも小さく、
平１ｕ度にも優れた原板が高歩留まりで得られる。また
調質圧延の圧延率の変化により、調質度Ｔ−１〜Ｔ”−
６と作り分けることができるので素材の統合が可能とな
り大きなメリットが得られる。As explained above, according to the present invention, the heat refining degree T-1 to T
- As a result of being able to manufacture grade 3 soft sheet metal sheets using CAL, the surface cleanliness is improved (Z), the variation in hardness is small,
Original plates with excellent flatness of 1u can be obtained with high yield. In addition, due to changes in the rolling rate of temper rolling, the temper degree is T-1 to T”-
Since it can be made separately from 6, it is possible to integrate materials, which provides a great advantage.
なお、上記圧延率をさらに高くすることによりＤＲ−８
，ＤＲ−９，ＤＲ−１０も得られる。またこの筒板は表
面清浄性に優れているので、Ｚｎめっき、Ｎｉめっき等
、広く表面処理鋼板に使っても、上記の特徴が発揮でき
る優れた鋼片を提供できる、等多大の効果が得られる。In addition, by further increasing the above rolling rate, DR-8
, DR-9 and DR-10 are also obtained. In addition, this cylindrical plate has excellent surface cleanliness, so even if it is used for a wide range of surface-treated steel sheets such as Zn plating and Ni plating, it can provide excellent steel pieces that exhibit the above characteristics, and many other effects can be obtained. It will be done.
第１図は、ｇＡ板のＣ含有１（ｗｔ％）と硬さ（ＨＲ−
３０Ｔ）との関係を示すグラフ、第２図は調質圧延の圧
延率（％）と硬さ（ＨＲ−３０Ｔ）との関係を示すグラ
フ、第３図はＮｂｉと再結晶温度との関係を示すグラフ
である。Figure 1 shows the C content 1 (wt%) and hardness (HR-
Figure 2 is a graph showing the relationship between temper rolling reduction (%) and hardness (HR-30T), Figure 3 is a graph showing the relationship between Nbi and recrystallization temperature. This is a graph showing.
Claims (1)
４％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％以下の成分を含有し、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５０以下にした後、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) Weight ratio: C: 0.004% or less, Si: 0.0
4% or less, Mn: 0.05-0.3%, S: 0.02%
Below, P: 0.02% or less, Al: 0.02 to 0.15
%, N: 0.004% or less, using a continuously cast steel billet with the remainder substantially consisting of Fe, hot rolling, pickling, cold rolling in the usual manner, and then continuous annealing. A steel sheet for cans, characterized in that the steel plate for cans has a desired degree of tempering by changing the rolling rate of the subsequent skin pass rolling after the steel plate has been subjected to a Rockwell hardness (HR-30T) of 50 or less. Method of manufacturing steel plates.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27208388A JPH02118024A (en) | 1988-10-28 | 1988-10-28 | Manufacture of steel sheet for can |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27208388A JPH02118024A (en) | 1988-10-28 | 1988-10-28 | Manufacture of steel sheet for can |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02118024A true JPH02118024A (en) | 1990-05-02 |
Family
ID=17508854
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27208388A Pending JPH02118024A (en) | 1988-10-28 | 1988-10-28 | Manufacture of steel sheet for can |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02118024A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008102899A1 (en) * | 2007-02-21 | 2008-08-28 | Jfe Steel Corporation | Processes for production of steel sheets for cans |
| 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 |
-
1988
- 1988-10-28 JP JP27208388A patent/JPH02118024A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008102899A1 (en) * | 2007-02-21 | 2008-08-28 | Jfe Steel Corporation | Processes for production of steel sheets for cans |
| JP2008202113A (en) * | 2007-02-21 | 2008-09-04 | Jfe Steel Kk | Manufacturing method of steel sheet for can |
| 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 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPH0152450B2 (en) | ||
| JPS593526B2 (en) | Manufacturing method of cold rolled steel sheet for deep drawing | |
| JPS5938336A (en) | Production of ultra thin steel sheet for can having high yield strength and drawability | |
| US3772091A (en) | Very thin steel sheet and method of producing same | |
| JPS6045690B2 (en) | Manufacturing method of ultra-thin steel sheet for cans with small in-plane anisotropy | |
| JP3826442B2 (en) | Manufacturing method of steel plate for can making with good workability and no rough skin | |
| JPS5938338A (en) | Production of ultra thin steel sheet having high yield strength and drawability | |
| JPH0341529B2 (en) | ||
| JPH02118024A (en) | Manufacture of steel sheet for can | |
| JPH02197523A (en) | Manufacture of steel sheet for can | |
| US5614034A (en) | Process for producing ultrahigh silicon electrical thin steel sheet by cold rolling | |
| JPS62161919A (en) | Manufacture of hard sheet steel for can excellent in drawability and minimized in anisotropy | |
| JPH02141536A (en) | Production of steel sheet for drawn can decreased earing | |
| JPH06306536A (en) | Surface treated original sheet for di can excellent in pressure withstanding strength and necked-in property and its production | |
| JPS6114216B2 (en) | ||
| JPS6330969B2 (en) | ||
| JPH02118026A (en) | Manufacture of steel sheet for can | |
| JPH02141535A (en) | Production of steel sheet for drawn can decreased earing | |
| JP3257390B2 (en) | Method for producing two-piece steel sheet with small in-plane anisotropy | |
| JP2980486B2 (en) | Manufacturing method of steel plate for non-aging low earring container | |
| JP3273383B2 (en) | Cold rolled steel sheet excellent in deep drawability and method for producing the same | |
| JPS6267119A (en) | Manufacture of steel sheet for di can having good flanging property and baking hardenability | |
| JPS60110845A (en) | Cold rolled steel sheet for enamel and its manufacture | |
| JPS5831035A (en) | Production of zinc hot dipped steel plate having excellent workability and baking hardenability | |
| JPH06306535A (en) | Surface treated original sheet for di can excellent in necked-in property and its production |