JPH0320414A - Production of non-ageing cold rolled steel sheet for porcelain enameling having superior workability - Google Patents
Production of non-ageing cold rolled steel sheet for porcelain enameling having superior workabilityInfo
- Publication number
- JPH0320414A JPH0320414A JP15634089A JP15634089A JPH0320414A JP H0320414 A JPH0320414 A JP H0320414A JP 15634089 A JP15634089 A JP 15634089A JP 15634089 A JP15634089 A JP 15634089A JP H0320414 A JPH0320414 A JP H0320414A
- Authority
- JP
- Japan
- Prior art keywords
- cold
- steel
- rolled steel
- slab
- workability
- 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
- 230000032683 aging Effects 0.000 title claims abstract description 15
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 11
- 238000004519 manufacturing process Methods 0.000 title claims description 20
- 238000004534 enameling Methods 0.000 title abstract description 6
- 229910052573 porcelain Inorganic materials 0.000 title abstract 3
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 43
- 239000010959 steel Substances 0.000 claims abstract description 43
- 238000000034 method Methods 0.000 claims abstract description 18
- 238000000137 annealing Methods 0.000 claims abstract description 16
- 238000010438 heat treatment Methods 0.000 claims abstract description 15
- 238000005098 hot rolling Methods 0.000 claims abstract description 13
- 238000005097 cold rolling Methods 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 238000001953 recrystallisation Methods 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract 3
- 210000003298 dental enamel Anatomy 0.000 claims description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 238000009749 continuous casting Methods 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 230000003679 aging effect Effects 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 230000001105 regulatory effect Effects 0.000 abstract description 4
- 239000000203 mixture Substances 0.000 abstract 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 7
- 239000000463 material Substances 0.000 description 5
- 150000003568 thioethers Chemical class 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000002195 synergetic effect Effects 0.000 description 2
- 241000473391 Archosargus rhomboidalis Species 0.000 description 1
- 229910000840 Capped steel Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001327 Rimmed steel Inorganic materials 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 210000000941 bile Anatomy 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009849 vacuum degassing Methods 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 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）
本発明は、良加工性非時効ホーロー用冷延綱板の製造方
法に関するものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial Field of Application) The present invention relates to a method for manufacturing a cold-rolled steel sheet for non-aging enamel with good workability.
（従来の技術）
従来の良加工性非時効ホーロー用鋼板はキャップド鋼又
はリムド綱を造塊、分塊、熱間圧延、冷間圧延の後オー
ブンコイル焼鈍法によって脱炭脱窒し、製造されてきた
。しかし、このようにして製造された良加工性非時効ホ
ーロー用鋼板は、造塊、分塊法によってスラブを製造す
る点や脱炭脱窒焼鈍が必要なことから製造コストが高い
という欠点があった。(Prior art) Conventional steel sheets for non-aging enameled steel with good workability are produced by decarburizing and denitrifying capped steel or rimmed steel by ingot-forming, blooming, hot rolling, cold rolling, and then decarburizing and denitrifying by oven coil annealing. It has been. However, the steel plate for non-aging enamel with good formability manufactured in this way has the disadvantage of high manufacturing cost because the slab is manufactured by agglomeration and blooming methods and decarburization and denitrification annealing is required. Ta.
そこで、製造コストの低下を図る目的で、連続鋳造法に
よって製造する方法が提案されている。Therefore, for the purpose of reducing manufacturing costs, a manufacturing method using a continuous casting method has been proposed.
例えば、特公昭５９−３４７６５号公報記載のように、
旧≦０． ４％で出鋼し、真空脱ガスでＣ≦０．０１％
とした後、Ｎｂ， Ｚｒ及びＲＥＭ： ０．０ １〜０
．１ ５％添加する方法があるが、高価なＲＥＭを添加
する必要があり製鋼コストの著しい上昇は避けられない
欠点が残る。For example, as described in Japanese Patent Publication No. 59-34765,
Old≦0. Steel is tapped at 4% and C≦0.01% by vacuum degassing.
After that, Nb, Zr and REM: 0.0 1~0
．． Although there is a method of adding 15%, the disadvantage remains that it is necessary to add expensive REM and a significant increase in steel manufacturing costs is unavoidable.
（発明が解決しようとする課題）
本発明は、前述したような従来のホーロー用鋼板の製造
法の問題点を克服し、加工性、非時効性、更に深絞り性
にも優れ、且つ、安価な連続鋳造法で高，価なＲＥＭを
添加しないで安価に製造できる良加工性非時効ホーロー
用鋼板の製造法を提供することを目的とする。(Problems to be Solved by the Invention) The present invention overcomes the problems of the conventional method of manufacturing steel sheets for enamel as described above, and has excellent workability, non-aging properties, and deep drawability, and is inexpensive. The purpose of the present invention is to provide a method for manufacturing a steel plate for non-aging enamel with good workability, which can be manufactured at low cost using a continuous casting method without adding expensive REM.
（課題を解決するための手段）
本発明は、従来のホーロー用鋼板が持つ欠点を克服する
ために検討を重ねて得られたもので、その要旨は下記の
通りである．
（１） Ｃ ： ０．０００５〜０．０１５％，
Ｓｔ， ０．０ ０ ３〜０．ｌＯ％． Ｍｎ：
０．０ ５〜２．０％，Ｐ：０．００１〜０． １ ０
０％，Ｓ：０．０６０〜０． ２ ５ ０％， ｓ
ｏｌ．ＩＪＯ． Ｏ Ｏ １〜０．１５％． Ｎ ：
０．０１００％以下，Ｔｉ：０．０３ 〜０．７０％、
且つ、（Ｍｎ＋ ５Ｔｉ） ／ Ｓ ： ５以上、残部
不可避的不純物及び鉄よりなる熔調を連続鋳造法にてス
ラブとし、１０００℃からｌ２５０゜Ｃのスラブ加熱温
度に加熱し、通常の熱間圧延を行い熱延鋼帯とし、５０
％以上の冷間圧延率で冷間圧延し、連続焼鈍法で再結晶
焼鈍を行うことを特徴とする良加工性非時効ホーロー用
冷延鋼板の製造方法。(Means for Solving the Problems) The present invention was obtained through repeated studies to overcome the drawbacks of conventional steel plates for enamel, and the gist thereof is as follows. (1) C: 0.0005-0.015%,
St, 0.0 0 3~0. lO%. Mn:
0.0 5-2.0%, P: 0.001-0. 1 0
0%, S: 0.060-0. 250%, s
ol. IJO. O O 1-0.15%. N:
0.0100% or less, Ti: 0.03 to 0.70%,
In addition, (Mn + 5Ti) / S: 5 or more, the melt consisting of unavoidable impurities and iron is made into a slab by continuous casting method, heated to a slab heating temperature of 1000 ° C to 1250 ° C, and then subjected to normal hot rolling. to make a hot-rolled steel strip, 50
A method for producing a cold-rolled steel sheet for non-aging enameling with good workability, characterized by cold rolling at a cold rolling rate of % or more and recrystallization annealing by a continuous annealing method.
（２） Ｃ ： ０．０００５〜０．０１５％，Ｓｉ
：０．００３〜０．１０％，Ｍｎ：０．０５〜２．０％
，Ｐ：０．００１〜０． １ ０ ０％，Ｓ：０．０６
０〜０． ２ ５ ０％，ｓｏｌ．Ａｌ０．００１〜０
．１５％． Ｎ ： ０．０１００％以下，Ｔｉ：０．
０３ 〜０．７０％、且つ、（Ｍｎ＋５Ｔｉ） ／Ｓ
： ５以上、残部不可避的不純物及び鉄よりなる溶鋼を
連続鋳造法にてスラブとし、ｉｏｏｏ゜Ｃから１１５０
℃のスラブ加熱温度に加熱し、通常の熱藺圧延を行い熱
延綱帯とし、５０％以上の冷間圧延率で冷間圧延し、連
続焼鈍法で再結晶焼鈍を行うことを特徴とする深絞り性
に優れた良加工性非時効ホーロー用冷延鋼板の製造方法
．
以下に本発明について詳細に述べる。(2) C: 0.0005-0.015%, Si
:0.003~0.10%, Mn:0.05~2.0%
, P: 0.001-0. 100%, S:0.06
0~0. 250%, sol. Al0.001~0
．． 15%. N: 0.0100% or less, Ti: 0.
03 ~0.70% and (Mn+5Ti)/S
: Molten steel consisting of 5 or more, the balance being unavoidable impurities and iron is made into a slab by continuous casting method,
It is characterized in that it is heated to a slab heating temperature of °C, subjected to normal hot rolling to form a hot rolled steel strip, cold rolled at a cold rolling rate of 50% or more, and recrystallized annealed using a continuous annealing method. A method for manufacturing cold-rolled steel sheets for non-aging enamel with excellent deep drawability and good formability. The present invention will be described in detail below.
本発明が目的とする良加工性非時効ホーロー用鋼板は、
製造方法を以下のように規制することによって得られる
。The steel plate for non-aging enamel with good workability, which is the object of the present invention, is as follows:
It can be obtained by regulating the manufacturing method as follows.
Ｃ含有量は、ｏ．ｏｏｏｓ〜０．０１５％でなければな
らない。Ｃ含有量が０． ０ １ ５％超になると硬質
化し、加工性が劣化するので上限を０．０１５％とした
。尚、下限を０．０００５％としたのは現在の製鋼法で
は製造不可能なためである。C content is o. Must be between ooos and 0.015%. C content is 0. If it exceeds 0.015%, it becomes hard and the workability deteriorates, so the upper limit was set at 0.015%. The lower limit is set to 0.0005% because it is impossible to manufacture with current steel manufacturing methods.
Ｓｉ含有量は、０． Ｏ Ｏ ３〜０．１０％でなけれ
ばならない。Ｓｔ含有量が０．１０％超になると硬質化
するので上限を０． １ ０％とした。尚、下限を０．
００３％としたのは現在の製鋼法では不可避的不純物と
して含有されるからである。The Si content is 0. O O should be between 3 and 0.10%. If the St content exceeds 0.10%, it will become hard, so the upper limit should be set at 0.1%. It was set at 10%. In addition, the lower limit is 0.
The reason why it is set at 0.003% is that it is contained as an unavoidable impurity in the current steel manufacturing method.
Ｍｎは重要な元素であり、その含有量は０．０５〜２．
０％で且つ、後述するＴｉおよびＳＮとの関係で、（Ｍ
ｎ＋ ５Ｔｉ） ／ Ｓ ： ５以上でなければならな
い．（Ｍｎ＋５Ｔｉ）／Ｓを５以上と過剰に添加するこ
とにより多量のＳ添加との相乗効果によって硫化物を粗
大化でき、その粗大硫化物によりホーロー性のなかでも
重要な耐爪飛び性が大幅に向上する。Mn is an important element, and its content ranges from 0.05 to 2.
0% and in relation to Ti and SN, which will be described later, (M
n+5Ti)/S: Must be 5 or more. By adding an excessive amount of (Mn+5Ti)/S of 5 or more, the sulfide can be coarsened due to the synergistic effect with the addition of a large amount of S, and the coarse sulfide greatly improves the nail chipping resistance, which is important in enamel properties. improves.
更に、硫化物が粗大化することにより析出物個数が極め
て少なくなり材質が硬化するのを防止できることが判明
した。但し、Ｍｎ含有量が２． ０％超になると固溶Ｍ
ｎ量が多くなり過ぎ材質が硬化するので上限を２． ０
％とした。尚、下限を０．０５％としたのは現在の製鋼
法では少なくとも０．０５％は不可避的不純物として含
有されるからである。Furthermore, it has been found that by coarsening the sulfide, the number of precipitates becomes extremely small, thereby preventing the material from hardening. However, if the Mn content is 2. If it exceeds 0%, solid solution M
If the amount of n becomes too large, the material will harden, so the upper limit is set to 2. 0
%. The lower limit is set to 0.05% because in the current steel manufacturing method, at least 0.05% of Ni is contained as an unavoidable impurity.
Ｐ含有量は、Ｏ． Ｏ Ｏ １〜０． １ ０ ０％で
なければならない。Ｐ含有量が０． １ ０ ０％超に
なると硬質化するので上限を０． １ ０ ０％とした
。尚、下限を０．００１％としたのは現在の製鋼法では
少なくとも０．００１％は不可避的不純物として含有さ
れるからである。The P content is O. O O 1-0. Must be 100%. P content is 0. If it exceeds 100%, it becomes hard, so the upper limit should be set at 0. It was set as 100%. Note that the lower limit is set to 0.001% because in the current steel manufacturing method, at least 0.001% is contained as an unavoidable impurity.
Ｓ含有量は、０． ０ ６ ０〜０． ２ ５ ０％で
なければならない。Ｓ含有量が０． ０ ６ ０％未満
では硫化物径を粗大化するのが困難となると共に、硫化
物の総量が不足する。その結果、十分なホーロー性が得
られなくなるので下限を０． ０ ６ ０％とした．又
、Ｓ含有量が０． ２ ５ ０％超になると硫化物総量
が多くなり過ぎ材質（α）の劣化が大きくなるので上限
を０． ２ ５ ０％とした。The S content is 0. 0 6 0~0. Must be 250%. S content is 0. If it is less than 0.60%, it becomes difficult to coarsen the sulfide diameter and the total amount of sulfide becomes insufficient. As a result, sufficient enamel quality cannot be obtained, so the lower limit is set to 0. It was set as 0.60%. Moreover, the S content is 0. If it exceeds 250%, the total amount of sulfides will become too large and the deterioration of the material (α) will increase, so the upper limit should be set at 0. It was set at 250%.
ｓｏｌ．ｆｉＪ含有量は、０． Ｏ Ｏ １〜０．１５
％でなければならない。ｓｏｔ． ｐｔ含有量が０．１
５％超になると硬質化するので上限を０．１５％とした
。尚、下限を０．００１％としたのは現在の製鋼法では
、仮令、Ｍ脱酸を行わなくとも耐火物等から入り不可避
的不純物として含有されるからである。sol. fiJ content is 0. O O 1-0.15
%Must. sot. pt content is 0.1
If it exceeds 5%, it becomes hard, so the upper limit was set at 0.15%. The lower limit was set at 0.001% because in the current steel manufacturing method, M is present as an unavoidable impurity from refractories even without deoxidizing.
Ｎ含有量は、ｏ．ｏｔｏｏ％以下でなければならない．
Ｎ含有量が０．０１００％超になると材質が硬化するの
で上限を０．０１００％とした。The N content is o. Must be less than or equal to too%.
If the N content exceeds 0.0100%, the material will harden, so the upper limit was set at 0.0100%.
↑ｉ含有量は、０．０３〜０．７０％でなければならな
い， Ｔｉ含有量が０．０３％未満では有害なＣを固定
するのに必要なＴｉ含有量が不足し、優れた非時効性や
加工性が得られなくなったり、ＴｔＳを形威してホーロ
ー性を向上させることが不十分となるので下限を０．０
３％にした．尚、上限を０．７０％としたのは、ホーロ
ー性の向上効果も飽和するばかりではなく、固溶強化に
より硬質化し加工性を損なう様になるので上限を０．７
０％とした。↑The i content must be between 0.03 and 0.70%. If the Ti content is less than 0.03%, the Ti content necessary to fix harmful C will be insufficient, resulting in excellent non-aging properties. The lower limit is set to 0.0 because it may not be possible to obtain good properties and workability, or it may be insufficient to improve the enamel properties by applying TtS.
I set it to 3%. The reason for setting the upper limit to 0.70% is that not only the effect of improving enamel properties is saturated, but also solid solution strengthening causes hardness and impairs workability.
It was set to 0%.
又、Ｔｉは、硫化物を形成するうえで重要な元素で、（
Ｍｎ＋５ Ｔｉ） ／ Ｓ ： ５以上でなければなら
ない，（Ｍｎ＋５↑ｉ）／Ｓを５以上と過剰に添加する
ことにより多量のＳ添加との相乗効果によって硫化物を
粗大化でき、その粗大硫化物により優れたホーロー性が
得られるようになる。In addition, Ti is an important element in forming sulfides (
Mn+5 Ti)/S: Must be 5 or more. By adding an excessive amount of (Mn+5↑i)/S of 5 or more, the sulfide can be coarsened due to the synergistic effect with the addition of a large amount of S, and the coarse sulfide This makes it possible to obtain superior enamel properties.
熱間圧延の条件はスラブ加熱温度条件以外は特に限定す
る必要がなく通常冷延鋼板に適用されている熱延条件で
良い。The hot rolling conditions do not need to be particularly limited except for the slab heating temperature conditions, and hot rolling conditions normally applied to cold rolled steel sheets may be used.
スラブ加熱温度は、１０００〜ｌ２５０゜Ｃでなければ
ならない．スラブ加熱温度が１２５０℃超になると、Ｓ
，Ｍｎ， Ｔｉを多量に添加しても硫化物を粗大化させ
ることが出来なくなり、微細化するようになる。その結
果、良好な加工性も、ホーロー性も得られなくなるので
上限のスラブ加熱温度を１２５０゜Ｃとした。The slab heating temperature must be 1000-1250°C. When the slab heating temperature exceeds 1250℃, S
, Mn, and Ti in large amounts, the sulfides cannot be coarsened and become finer. As a result, neither good workability nor porosity could be obtained, so the upper limit slab heating temperature was set at 1250°C.
尚、スラブ加熱温度の下限を１０００℃としたのは１０
００゜Ｃ未満のスラブ加熱温度では熱間圧延の仕上げ温
度が低下し熱延できなくなるからである．更に、優れた
深絞り性を得る方法についても種々検討した．深絞り性
にも優れた良゛加工性非時効ホーロー用鯛板を製造する
場合は、熱間圧延に際し、１０００〜１１５０゜Ｃのス
ラブ加熱温度に加熱し熱間圧延を行えば良い。スラブ加
熱温度が１１５０℃超と高い場合に一部生戒する比較的
細かなＭｎＳをも粗大化でき、深絞り性にも優れた良加
工性非時効ホーロー用鋼板が製造できる。Furthermore, the lower limit of the slab heating temperature was set at 1000°C.
This is because if the slab heating temperature is less than 00°C, the finishing temperature of hot rolling will drop and hot rolling will not be possible. Furthermore, various methods for obtaining excellent deep drawability were investigated. When producing a non-aged enameled sea bream plate with excellent deep drawability and good workability, hot rolling may be carried out by heating the slab to a slab heating temperature of 1000 to 1150°C. It is possible to coarsen relatively fine MnS, which is partially avoided when the slab heating temperature is as high as 1150° C., and to produce a steel plate for non-aging enamel with good workability and excellent deep drawability.
冷間圧延は、５０％以上の冷間圧延率で圧延すれば良い
．冷間圧延率が５０％未満になると連続焼鈍時の再結晶
温度が上昇したり、冷延鋼板として必要な深絞り性を示
すｆ値が低下し、冷延鋼板としての加工性が得られなく
なるので下限の冷間圧延率を５０％とした。上限は特に
限定する必要がないので規制しない。Cold rolling may be performed at a cold rolling rate of 50% or more. If the cold rolling reduction is less than 50%, the recrystallization temperature during continuous annealing will increase, the f value, which indicates the deep drawability necessary for a cold rolled steel sheet, will decrease, and the workability of a cold rolled steel sheet will not be obtained. Therefore, the lower limit cold rolling rate was set to 50%. There is no need to specifically limit the upper limit, so it is not regulated.
連続焼鈍は、通常行われている再結晶焼鈍であれば、良
加工性非時効ホーロー用鋼板が製造できるので特に限定
する必要はない。Continuous annealing does not need to be particularly limited as long as it is recrystallization annealing that is commonly performed, since a steel plate for non-aging enamel with good workability can be produced.
又、調質圧延は、特に規制する必要がなく必要に応じ施
せば良い。Further, temper rolling does not need to be particularly regulated and may be performed as necessary.
（実施例） 以下に本発明の効果を実施例により説明する。(Example) The effects of the present invention will be explained below using examples.
く実施例−１〉
所定の威分の鋼を連続鋳造法で鋳片とし、第１表に示す
条件で連続熱延し巻き取った熱延鋼帯を８０％の冷延率
で０． ８ ０ ｍｍの冷延板にし、７８０”ＣＸ６０
ｓｅｃの連続焼鈍をした後０．８％の調質圧延を施し、
ホーロー用鋼板を製造した。第１表に威分及び熱延条件
を、第２表に製造したホーロー用鋼板の材質並びに爪飛
び試験結果を示す。Embodiment 1 A hot-rolled steel strip made of steel of a predetermined weight was made into a slab by a continuous casting method, continuously hot-rolled under the conditions shown in Table 1, and wound up at a cold-rolling rate of 80%. 80 mm cold-rolled plate, 780”CX60
After continuous annealing for sec, 0.8% temper rolling was performed,
Manufactured steel plates for enamel. Table 1 shows the strength and hot rolling conditions, and Table 2 shows the material of the manufactured steel plate for enamel and the results of the nail fly test.
尚、爪飛び試験は、胆脂一酸洗一施釉一焼戒（８３０゜
ＣＸ３ｍｉｎ）を行ない、爪飛び発生状況を調査した。In the nail-flying test, bile fat, pickling, glazing, and firing (830°C x 3 min) were performed to investigate the occurrence of nail-flying.
鋼１は、Ｓを添加しない通常の極低炭素Ｔｉ添加冷延鋼
板の比較例である。加工性を示す機械試験値は何れも優
れた特性となっているが、爪飛びが多発し、ホーロー用
鋼板としては使用できない．鋼２は（Ｍｎ ＋ ５ Ｔ
ｉ ） ／ Ｓが５未満の比較例である。（Ｍｎ＋５Ｔ
ｉ） ／Ｓ−４．４と低いため、機械的性質が極めて悪
い。又、ＴｉがＴｉＳとなるためＣを固定するのに必要
なＴｉが不足するようになってＹ．Ｐ −Ｅｆ ＝ １
． ５％発生し非時効性も確保できていない。Steel 1 is a comparative example of a normal ultra-low carbon Ti-added cold-rolled steel sheet without adding S. Although the mechanical test values indicating workability are all excellent, there are frequent occurrences of nail skipping, making it unusable as a steel plate for enamel. Steel 2 is (Mn + 5 T
i) This is a comparative example in which /S is less than 5. (Mn+5T
i) Since the /S-4.4 is low, the mechanical properties are extremely poor. In addition, since Ti becomes TiS, the amount of Ti necessary to fix C becomes insufficient, and Y. P-Ef = 1
．． 5%, and non-prescription property has not been ensured.
鋼３．鋼４．１１５，鋼６は、本発明の考え方に則って
Ｓを多量に添加し、硫化物を粗大化した良加工性非時効
ホーロー用鋼板の本発明の実施例である。機械的性質及
びホーロー特性はいずれも良好な値を示し非時効性も確
保できている。Steel 3. Steel 4.115 and Steel 6 are examples of the present invention of steel plates for non-aging enamel with good workability, in which a large amount of S is added in accordance with the concept of the present invention to coarsen sulfides. Both mechanical properties and enamel properties showed good values, and non-aging properties were also ensured.
鋼３は、請求項１の低温巻取の実施例で機械的性質及び
ホーロー特性はいずれも良好な値を示し非時効性も確保
できている。鋼４は、加工性を向上させるため高温巻取
を行った実施例で、加工性が向上している。鋼６も加工
性を向上させるため高温巻取を行った実施例で、Ｓ含有
量が０． １ ５ ２％と高いわりには良好な加工性が
得られている。Steel 3 is an example of low-temperature winding according to claim 1, and exhibits good values for both mechanical properties and enamel properties, and also ensures non-aging properties. Steel 4 is an example in which high-temperature coiling was performed to improve workability, and the workability is improved. Steel 6 is also an example in which high-temperature coiling was performed to improve workability, and the S content was 0. Good workability was obtained despite the high value of 152%.
鋼５は、低温スラブ加熱を行った請求項２の実施例で、
Ｙ．Ｐ． １１！のみならず深絞り性を示す７が顕著
に向上している。Steel 5 is an embodiment of claim 2 in which low-temperature slab heating was performed,
Y. P. 11! In addition, 7, which shows deep drawability, was significantly improved.
綱７は、本発明の範囲を超えてＳを多量に添加した比較
例である。ホーロー特性は良好であるが機械的性質が大
きく劣化している。Steel No. 7 is a comparative example in which S was added in a large amount beyond the scope of the present invention. The enamel properties are good, but the mechanical properties are significantly deteriorated.
（発明の効果）
以上の実施例に示すように、本発明の良加工性非時効ホ
ーロー用鋼板の製造方法は、ホーロー性にも優れ、又、
加工性にも優れた発明であり、工業的に価値のある発明
である。(Effects of the Invention) As shown in the above examples, the method for manufacturing a steel plate for non-aging enameling with good workability of the present invention has excellent enameling properties, and
This invention has excellent processability and is industrially valuable.
Claims (2)
０３〜０．１０％、Ｍｎ：０．０５〜２．０％、Ｐ：０
．００１〜０．１００％、Ｓ：０．０６０〜０．２５０
％、ｓｏｌ．Ａｌ０．００１〜０．１５％、Ｎ：０．０
１００％以下、Ｔｉ：０．０３〜０．７０％、且つ、（
Ｍｎ＋５Ｔｉ）／Ｓ：５以上、残部不可避的不純物及び
鉄よりなる溶鋼を連続鋳造法にてスラブとし、１０００
℃から１２５０℃のスラブ加熱温度に加熱し、通常の熱
間圧延を行い熱延鋼帯とし、５０％以上の冷間圧延率で
冷間圧延し、連続焼鈍法で再結晶焼鈍を行うことを特徴
とする良加工性非時効ホーロー用冷延鋼板の製造方法。(1) C: 0.0005-0.015%, Si: 0.0
03-0.10%, Mn: 0.05-2.0%, P: 0
．． 001~0.100%, S:0.060~0.250
%, sol. Al0.001-0.15%, N:0.0
100% or less, Ti: 0.03 to 0.70%, and (
Molten steel consisting of Mn+5Ti)/S:5 or more, the remainder consisting of unavoidable impurities and iron is made into a slab by continuous casting, and 1000
℃ to a slab heating temperature of 1250℃, perform normal hot rolling to obtain a hot rolled steel strip, cold roll at a cold rolling rate of 50% or more, and perform recrystallization annealing using a continuous annealing method. A method for producing cold-rolled steel sheets for non-aging enamel with good workability.
０３〜０．１０％、Ｍｎ：０．０５〜２．０％、Ｐ：０
．００１〜０．１００％、Ｓ：０．０６０〜０．２５０
％、ｓｏｌ．Ａｌ０．００１〜０．１５％、Ｎ：０．０
１００％以下、Ｔｉ：０．０３〜０．７０％、且つ、（
Ｍｎ＋５Ｔｉ）／Ｓ：５以上、残部不可避的不純物及び
鉄よりなる溶鋼を連続鋳造法にてスラブとし、１０００
℃から１１５０℃のスラブ加熱温度に加熱し、通常の熱
間圧延を行い熱延鋼帯とし、５０％以上の冷間圧延率で
冷間圧延し、連続焼鈍法で再結晶焼鈍を行うことを特徴
とする深絞り性に優れた良加工性非時効ホーロー用冷延
鋼板の製造方法。(2) C: 0.0005-0.015%, Si: 0.0
03-0.10%, Mn: 0.05-2.0%, P: 0
．． 001~0.100%, S:0.060~0.250
%, sol. Al0.001-0.15%, N:0.0
100% or less, Ti: 0.03 to 0.70%, and (
Molten steel consisting of Mn+5Ti)/S:5 or more, the remainder consisting of unavoidable impurities and iron is made into a slab by continuous casting, and 1000
℃ to 1150℃ slab heating temperature, perform normal hot rolling to obtain a hot rolled steel strip, cold roll at a cold rolling rate of 50% or more, and perform recrystallization annealing using a continuous annealing method. A method for producing cold-rolled steel sheets for non-aging enamel with excellent deep drawability and good workability.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15634089A JPH0320414A (en) | 1989-06-19 | 1989-06-19 | Production of non-ageing cold rolled steel sheet for porcelain enameling having superior workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15634089A JPH0320414A (en) | 1989-06-19 | 1989-06-19 | Production of non-ageing cold rolled steel sheet for porcelain enameling having superior workability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0320414A true JPH0320414A (en) | 1991-01-29 |
Family
ID=15625631
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15634089A Pending JPH0320414A (en) | 1989-06-19 | 1989-06-19 | Production of non-ageing cold rolled steel sheet for porcelain enameling having superior workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0320414A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100347570B1 (en) * | 1997-08-29 | 2002-09-18 | 주식회사 포스코 | Method for manufacturing steel sheet for enameled ironware with excellent formability and surface property |
| WO2010018906A1 (en) * | 2008-08-14 | 2010-02-18 | 주식회사 포스코 | Steel sheet for enamelling, and a production method therefor |
| KR100951256B1 (en) * | 2002-12-27 | 2010-04-02 | 주식회사 포스코 | Method of manufacturing hot rolled steel sheet for porcelain enameling |
| CN108048735A (en) * | 2017-11-23 | 2018-05-18 | 首钢集团有限公司 | Cold rolling enamel sheet and its production method |
| CN109652739A (en) * | 2019-01-22 | 2019-04-19 | 山东钢铁股份有限公司 | A kind of enamel high intensity cold strip rolling and preparation method thereof |
-
1989
- 1989-06-19 JP JP15634089A patent/JPH0320414A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100347570B1 (en) * | 1997-08-29 | 2002-09-18 | 주식회사 포스코 | Method for manufacturing steel sheet for enameled ironware with excellent formability and surface property |
| KR100951256B1 (en) * | 2002-12-27 | 2010-04-02 | 주식회사 포스코 | Method of manufacturing hot rolled steel sheet for porcelain enameling |
| WO2010018906A1 (en) * | 2008-08-14 | 2010-02-18 | 주식회사 포스코 | Steel sheet for enamelling, and a production method therefor |
| JP2011530658A (en) * | 2008-08-14 | 2011-12-22 | ポスコ | Steel plate for enamel and method for producing the same |
| CN108048735A (en) * | 2017-11-23 | 2018-05-18 | 首钢集团有限公司 | Cold rolling enamel sheet and its production method |
| CN109652739A (en) * | 2019-01-22 | 2019-04-19 | 山东钢铁股份有限公司 | A kind of enamel high intensity cold strip rolling and preparation method thereof |
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