JPH0217614B2 - - Google Patents
Info
- Publication number
- JPH0217614B2 JPH0217614B2 JP19842781A JP19842781A JPH0217614B2 JP H0217614 B2 JPH0217614 B2 JP H0217614B2 JP 19842781 A JP19842781 A JP 19842781A JP 19842781 A JP19842781 A JP 19842781A JP H0217614 B2 JPH0217614 B2 JP H0217614B2
- Authority
- JP
- Japan
- Prior art keywords
- steel
- rolled
- cold
- hot
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- 229910000831 Steel Inorganic materials 0.000 claims description 39
- 239000010959 steel Substances 0.000 claims description 39
- 238000010438 heat treatment Methods 0.000 claims description 19
- 238000000137 annealing Methods 0.000 claims description 18
- 238000000034 method Methods 0.000 claims description 15
- 239000010960 cold rolled steel Substances 0.000 claims description 11
- 238000009749 continuous casting Methods 0.000 claims description 11
- 238000005098 hot rolling Methods 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 238000005097 cold rolling Methods 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 239000000463 material Substances 0.000 description 13
- 238000005096 rolling process Methods 0.000 description 10
- 230000000694 effects Effects 0.000 description 7
- 238000001953 recrystallisation Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 230000003746 surface roughness Effects 0.000 description 5
- 238000003303 reheating Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 3
- 238000009628 steelmaking Methods 0.000 description 3
- 238000004140 cleaning Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000009849 vacuum degassing Methods 0.000 description 2
- 229910000840 Capped steel Inorganic materials 0.000 description 1
- 206010013786 Dry skin Diseases 0.000 description 1
- 229910000655 Killed steel Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 230000002829 reductive effect Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Continuous Casting (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
本発明は加工用連続鋳造冷延鋼板の製造方法に
関するものである。
従来冷延鋼板素材として表面性状が良好なリム
ド、キヤツプド鋼が主として用いられて来たが、
連続鋳造技術の進歩により鋳片の表面、内部性状
ともに大幅に改善され、コスト、均質性に優れた
連鋳材に移行して来ている。
連鋳材の冷延板素材にはAlキルド、Siキルド
鋼などが使われて来たが、従来のリムド・キヤツ
プド鋼の特性を全て代替できていない。すなわ
ち、加工性、硬度、冷延板テンパーカラー、亜鉛
メツキ密着性、浸炭焼入性などに問題があり、こ
れらの特性を満し得るAl、Nレベルが低い(Al
0.02%、N40ppm)鋼種(以下低Al鋼と呼
ぶ)が要求される。低Al鋼はリムド・キヤツプ
ド鋼が使用されていた広い用途に適用できるが、
箱焼鈍材においてコイル外周部を加工する際肌荒
れが生じ易いという問題を生ずる。この理由は低
Al鋼においては、Alの歩留、適中精度を向上さ
せるため真空脱ガス処理が一般的に行われる。し
たがつて低Al鋼中の酸素レベルはリムド・キヤ
ツプド鋼よりはるかに低く、酸化物系介在物が少
いいわゆる清浄鋼となる。この場合の低Al鋼焼
鈍時の再結晶挙動は通常Alキルド鋼と異なり延
伸粒を生ぜず、Al窒化物は一次再結晶粒抑制効
果を示すため細粒でまたN固定が十分でないため
硬質になり易い。これらを改善するため焼鈍温度
を上昇させると、コイル外周部のように高温度に
長時間置かれる部分では、比較的大きな粒を核と
して著しい結晶粒の粗大化を起し、加工時に肌荒
れを生ずるため加工用鋼板には不適当となる。
発明者らは低Al鋼箱焼鈍時に結晶粒の粗大化
が起らない方法を種々研究した結果、連続鋳造鋳
片を高温状態から直接圧延または保熱、軽加熱の
単独あるいは組合せた工程を経た後に圧延しした
熱延鋼帯を冷延素材とした場合、従来の再加熱後
圧延された熱延鋼帯を使用した場合に生じる箱焼
鈍時の肌荒れが防止される場合があることを明ら
かにし、この知見を用いて加工用低Al連鋳冷延
鋼板を発明するに至つた。
すなわち本発明を構成するところは、C0.03〜
0.07%、Mn0.22〜0.35%、Al、Nを第1図のイに
示す範囲すなわち座標点a,b,c,d,e,
f,g,hで囲まれる範囲含有し、残部が鉄およ
び不可避不純物からなる鋼を連続鋳造して得られ
る高温鋳片を直接、もしくは該高温鋳片を保熱工
程または軽加熱工程のいずれかもしくは保熱およ
び軽加熱の両工程を経たのち、Ar3点以上の温度
で熱間圧延した熱延鋼帯を酸洗又は他の手段で脱
スケールした後冷延し、箱焼鈍することを特徴と
する加工用連続鋳造冷延鋼板の製造方法である。
以下本発明の構成要件の限定理由を説明する。
Cは加工用冷延鋼板であつては加工性の点から低
くなければならず上限は0.07%となる。一方下限
はCが低過ぎると肌荒れが著しく発生し易くなる
ので0.03%以上が必要である。Mnの上限は硬化
および延性低下を防ぐため0.35%に、下限は通常
量のS量(約0.015%)による熱間加工性低下防
止に必要な最小量(Sの15倍)から0.22%とな
る。Al、Nは本発明において添加量の適正値が
組合せ効果として決まるため、その適正範囲を第
1図に示した。
図において横軸はAl含有量(単位10-3%)、縦
軸はN含有量(単位ppm)であり、その適正な範
囲は斜線で示すイの範囲すなわちa(7、40)、b
(15、40)、c(15、28)、d(22、20)、e(30、
20)、f(30、12)、g(15、12)、h(7、17)の各
座標点で囲まれる範囲である。このAl、N量の
範囲が連続鋳片の直接圧延または軽加熱または保
熱および軽加熱後圧延した(以下直接圧延などと
総称する)熱延鋼帯では、冷延板の箱焼鈍時に結
晶粒の粗大化が防止されることを第2図に示し
た。第2図は上記条件の熱延鋼帯と通常再加熱工
程による熱延鋼帯から製造した冷延板(冷延率70
%)を、750℃×6hr焼鈍したときの結晶粗大化
(肌荒れ発生)状況を示す。
これらのことから連続鋳造後直接圧延などを行
うときは上記のAl、N量の範囲イで焼鈍時に粗
大粒は発生しないが、再加熱材では粗粒化する。
本発明のAl、Nの範囲より右上の範囲ロは連鋳
後再加熱を行つた場合にも結晶が粗大化しない本
発明でのべる連鋳後の直接圧延などの効果を特別
に必要としない範囲、また左下の範囲ハは本発明
の連鋳後の直接圧延などによる粗粒化防止効果が
およばない範囲であつて、ともに本発明のAl、
N範囲に含まれない。
本発明において製鋼・熱延の工程が中心をなす
要件であり、本発明でのべる直接圧延が可能な設
備配置を必要とする製鋼においては、通常の製鋼
炉を用いて上記成分鋼を溶製、脱酸成分調整され
るが、この過程で真空脱ガス装置を用いることは
差支えない。このようにして得られた溶鋼を連続
鋳片が直接、鋳片を短時間保熱する工程、
鋳片の均熱化のため行う軽加熱工程、保熱・軽
加熱を組合せた工程のいずれかを経た後に熱延設
備に送られて圧延されることが本発明の必須構成
条件となることは先に説明した。こゝで短時間保
熱とは通常の加熱時間よりはるかに短いせいぜい
1時間以内で鋳片自身の保有熱により温度を均一
化し温度の低下を防止するため、鋳片移送ライン
に設けられた例えば保護カバーまたはその他の保
熱手段を用いた保熱を意味する。また均熱のため
軽加熱とは鋳片表面または端部など温度が低下し
た部分を局部的に急速に加熱するための例えばガ
スバーナーまたは誘導加熱などの手段による加熱
である。
以上の熱延は各鋼のAr3点以上の温度で行われ
るが、これは熱延温度が低下すると冷延鋼板の材
質下を招くからである。上記の方法で製造された
熱延鋼帯は通常の酸洗などの脱スケール後、冷延
率40〜90%、好ましくは50〜80%で冷延し、更に
必要に応じて種々の洗浄方法で洗浄化した後、箱
焼鈍が行われる。このときの焼鈍条件は加工用の
冷延鋼板の材質レベルを満足するために必要な温
度・時間から決定される。
こゝで同一のAl、N量であるのに熱延前のプ
ロセスの差が冷延鋼板材質を決定する焼鈍時に現
われる理由は次のように考えられる。先づ低Al
鋼で高温長時間の焼鈍(コイル外周部相当)時に
結晶粒が異常に成長する現象は二次再結晶と呼ば
れており、一次再結晶が微細でしかもその中に粗
い粒が含まれているときに生じ易い。本発明鋼と
同一成分鋼を再加熱工程で製造した熱延鋼帯から
得られた冷延板は、熱延板中または焼鈍加熱時に
析出する微細なAlNにより一次再結晶粒の成長
が抑制され二次再結晶が起り易い状態となる。こ
れに対しては直接圧延などで製造された熱延板中
のAlN析出はほとんどなく焼鈍加熱中の析出も
おくれるため、一次再結晶粒の成長はAlNによ
つて妨げられず、二次再結晶が起り難くなる。こ
のようにしてAl、N量と熱延前の製造前のプロ
セスが相互に関係して本発明の効果をもたらして
いることが理解される。
次に本発明の効果を実施例により説明する。
第1表に供試鋼成分・プロセス・熱延条件およ
び焼鈍による肌荒れ発生部(加工用途向不合格
部)長さを示す。なおこの実施例における熱延板
板厚は2.7mm、冷延率70%(冷延板板厚0.8mm)、
焼鈍条件は700℃で4時間の箱焼鈍である。鋼A
はAl、N量が本発明の範囲より高くて従来の再
加熱圧延された素材によつても肌荒れ発生が小さ
いが、この例は高温鋳片を保熱・軽加熱して熱延
した素材を用いた場合である。鋼C,Eはそれぞ
れ同一成分の再加熱圧延された比較鋼B,Dの肌
荒れ発生が著しいのに対し、素材の連鋳高温鋳片
の軽加熱または保熱後圧延した効果により肌荒れ
発生が小さくなつている。鋼FはAl量が低いた
め、連鋳高温鋳片の軽加熱後の圧延で得られた素
材によつても肌荒れ発生が防げなかつた例であ
る。
第2表は第1表と同一鋼板の機械的性質(コイ
ル内平均値)を示す。本発明鋼は比較鋼Aと同等
程度の機械的性質を示しており、加工用冷延鋼板
として充分な特性を示している。
以上で詳細に述べたように本発明は比較的低い
量のAl、Nを含み、連続鋳造後の高温鋳片を直
接または保熱・軽加熱工程のいずれかまたは両方
を経た後に熱延した鋼帯を素材とした冷延鋼板の
製造方法であつて、箱焼鈍時の異常粗大粒発生に
よる歩留低下が小さく、材質が優れているとゝも
に、鋳片再加熱工程省略による燃料コストの低
減、省力省工程化などのコスト低下メリツトが大
きい経済的にも優れた方法である。
The present invention relates to a method for producing a continuous cast cold rolled steel sheet for processing. Traditionally, rimmed and capped steels with good surface properties have been mainly used as materials for cold-rolled steel sheets.
Advances in continuous casting technology have significantly improved both the surface and internal properties of slabs, leading to a transition to continuous casting materials that are superior in cost and homogeneity. Al-killed and Si-killed steels have been used as cold-rolled plate materials for continuous casting, but they have not been able to replace all of the properties of conventional rimmed and capped steels. In other words, there are problems with workability, hardness, cold-rolled plate temper color, galvanizing adhesion, carburizing hardenability, etc., and the Al and N levels that can satisfy these characteristics are low (Al
0.02%, N40ppm) steel type (hereinafter referred to as low-Al steel) is required. Low-Al steel can be applied to a wide range of applications where rimmed and capped steels were used;
When processing the outer periphery of a coil in a box annealed material, a problem arises in that roughness tends to occur. The reason for this is low
For Al steel, vacuum degassing treatment is generally performed to improve Al yield and accuracy. Therefore, the oxygen level in low-Al steel is much lower than in rimmed capped steel, making it a so-called clean steel with fewer oxide inclusions. In this case, the recrystallization behavior during annealing of low-Al steel is different from normal Al-killed steel, in that it does not produce elongated grains, and Al nitrides exhibit a primary recrystallization grain suppressing effect, resulting in fine grains and insufficient N fixation, resulting in hardness. It's easy. If the annealing temperature is increased to improve these problems, in parts such as the outer periphery of the coil that are exposed to high temperatures for a long period of time, the crystal grains will coarsen considerably with relatively large grains as cores, resulting in rough skin during processing. Therefore, it is unsuitable for processing steel sheets. The inventors researched various methods to prevent coarsening of grains during annealing of low-Al steel boxes, and found that continuous cast slabs were directly rolled from high-temperature conditions, or subjected to heat retention and light heating alone or in combination. It was revealed that when a hot-rolled steel strip that has been subsequently rolled is used as a cold-rolled material, roughness during box annealing that occurs when using a conventional hot-rolled steel strip that has been rolled after reheating may be prevented. Using this knowledge, we invented a low-Al continuous cast cold-rolled steel sheet for machining. In other words, what constitutes the present invention is C0.03~
0.07%, Mn 0.22~0.35%, Al, and N in the range shown in Figure 1 A, that is, coordinate points a, b, c, d, e,
A high-temperature slab obtained by continuous casting of steel containing the range surrounded by f, g, and h with the remainder consisting of iron and unavoidable impurities is directly cast, or the high-temperature slab is subjected to either a heat retention process or a light heating process. Alternatively, after passing through both heat retention and light heating processes, hot rolled steel strip is hot rolled at a temperature of Ar 3 or higher, descaled by pickling or other means, cold rolled, and box annealed. This is a method for producing continuously cast cold rolled steel sheets for processing. The reasons for limiting the constituent elements of the present invention will be explained below.
In cold-rolled steel sheets for processing, C must be low from the viewpoint of workability, and the upper limit is 0.07%. On the other hand, the lower limit needs to be 0.03% or more because if C is too low, skin roughness is likely to occur significantly. The upper limit of Mn is 0.35% to prevent hardening and deterioration of ductility, and the lower limit is 0.22% from the minimum amount (15 times S) required to prevent deterioration of hot workability due to the normal amount of S (approximately 0.015%). . In the present invention, the appropriate values of the addition amounts of Al and N are determined as a combination effect, and the appropriate ranges are shown in FIG. In the figure, the horizontal axis is the Al content (unit: 10 -3 %), and the vertical axis is the N content (unit: ppm), and the appropriate range is the shaded range a (7, 40), b
(15, 40), c (15, 28), d (22, 20), e (30,
20), f (30, 12), g (15, 12), and h (7, 17). In hot-rolled steel strips that are formed by direct rolling of continuous slabs or by light heating or heat retention and rolling after light heating (hereinafter collectively referred to as direct rolling, etc.), crystal grains are formed during box annealing of cold-rolled sheets. Figure 2 shows that the coarsening of the particles is prevented. Figure 2 shows a cold-rolled sheet manufactured from a hot-rolled steel strip under the above conditions and a hot-rolled steel strip subjected to a normal reheating process (cold rolling rate: 70
%) is annealed at 750°C for 6 hours. For these reasons, when performing direct rolling after continuous casting, coarse grains are not generated during annealing when the Al and N amounts are in the above range A, but coarse grains occur in the reheated material.
The upper right range B of the Al and N ranges of the present invention is a range in which the crystals do not become coarse even when reheated after continuous casting, and there is no special need for effects such as direct rolling after continuous casting, which is described in the present invention. , and the lower left range C is a range in which the effect of preventing grain coarsening by direct rolling after continuous casting of the present invention does not reach, and both are the range where Al,
Not included in N range. In the present invention, the steelmaking and hot rolling processes are the main requirements, and in steelmaking that requires an equipment arrangement that allows direct rolling as described in the present invention, the above component steel is melted using an ordinary steelmaking furnace. Although the deoxidizing components are adjusted, a vacuum degassing device may be used in this process. A process in which the molten steel obtained in this way is directly heated by a continuous slab for a short period of time,
It is an essential condition of the present invention that the slab be sent to a hot rolling facility and rolled after going through either a light heating process for soaking the slab or a process that combines heat retention and light heating. I explained it earlier. In this case, short-term heat retention is a heating process installed in the slab transfer line, for example, in order to equalize the temperature by using the heat retained in the slab itself within one hour, which is much shorter than the normal heating time, and to prevent a drop in temperature. means heat retention using a protective cover or other heat retention means. Furthermore, light heating for uniform heating refers to heating using a means such as a gas burner or induction heating to locally rapidly heat a portion where the temperature has decreased, such as the surface or end of the slab. The above hot rolling is carried out at a temperature of 3 or more Ar points for each steel, because if the hot rolling temperature decreases, the material quality of the cold rolled steel sheet deteriorates. The hot rolled steel strip produced by the above method is descaled by ordinary pickling, etc., then cold rolled at a cold rolling ratio of 40 to 90%, preferably 50 to 80%, and further subjected to various cleaning methods as necessary. After cleaning, box annealing is performed. The annealing conditions at this time are determined from the temperature and time necessary to satisfy the material quality level of the cold rolled steel plate for processing. The reason why differences in the process before hot rolling appear during annealing, which determines the material quality of the cold rolled steel sheet, is thought to be as follows, even though the amounts of Al and N are the same. First low Al
The phenomenon in which crystal grains grow abnormally during high-temperature, long-term annealing (corresponding to the outer circumference of a coil) in steel is called secondary recrystallization, and the primary recrystallization is fine, but it contains coarse grains. It can sometimes occur. In cold-rolled sheets obtained from hot-rolled steel strips produced by reheating steel with the same composition as the steel of the present invention, the growth of primary recrystallized grains is suppressed by fine AlN precipitated in the hot-rolled sheets or during annealing. This creates a state in which secondary recrystallization is likely to occur. On the other hand, there is almost no AlN precipitation in hot-rolled sheets manufactured by direct rolling, and precipitation during annealing is delayed, so the growth of primary recrystallized grains is not hindered by AlN, and secondary recrystallization Crystals are less likely to form. In this way, it is understood that the amounts of Al and N and the pre-manufacturing process before hot rolling are interrelated to bring about the effects of the present invention. Next, the effects of the present invention will be explained using examples. Table 1 shows the sample steel composition, process, hot rolling conditions, and length of the part where surface roughness occurs due to annealing (part rejected for processing purposes). In this example, the hot rolled sheet thickness was 2.7 mm, the cold rolling rate was 70% (cold rolled sheet thickness 0.8 mm),
The annealing conditions are box annealing at 700°C for 4 hours. Steel A
The Al and N contents are higher than the range of the present invention, and surface roughness is small even with the conventional reheat-rolled material, but in this example, the material is hot-rolled by retaining and lightly heating a high-temperature cast slab. This is the case when it is used. In contrast to steels C and E, which have the same composition and are reheated and rolled for comparative steels B and D, the occurrence of surface roughness is significant, whereas the occurrence of surface roughness is small due to the effect of lightly heating the continuous cast high-temperature slab of the raw material or rolling it after heat retention. It's summery. Since Steel F has a low Al content, this is an example in which the occurrence of surface roughness could not be prevented even with the material obtained by lightly heating and rolling a continuously cast high-temperature slab. Table 2 shows the mechanical properties (average values within the coil) of the same steel sheets as in Table 1. The steel of the present invention exhibits mechanical properties comparable to those of Comparative Steel A, and exhibits sufficient properties as a cold-rolled steel sheet for processing. As described in detail above, the present invention is a steel that contains relatively low amounts of Al and N and is hot-rolled from a high-temperature slab after continuous casting or after passing through one or both of heat retention and light heating processes. This is a manufacturing method for cold-rolled steel sheets using strips as raw materials.The yield loss due to the generation of abnormally coarse grains during box annealing is small, the material quality is excellent, and fuel costs are reduced by omitting the slab reheating process. It is an economically excellent method that has great cost reduction benefits such as reduction in production costs, labor savings, and process savings.
【表】【table】
【表】【table】
第1図は本発明に用いられる鋼のAl、Nの範
囲を示す図、第2図はAl、Nの範囲、熱延鋼帯
製造プロセスと750゜×6時間の箱焼鈍条件におけ
る異常粗大粒(肌荒)発生状況の関係を示す図で
ある。
Figure 1 shows the range of Al and N in the steel used in the present invention, Figure 2 shows the range of Al and N, the hot rolled steel strip manufacturing process, and abnormal coarse grains in the 750° x 6 hour box annealing conditions. (Rough skin) is a diagram showing the relationship between occurrence conditions.
Claims (1)
第1図の座標点a,b,c,d,e,f,g,h
で囲まれる範囲を含有し、残部が鉄および不可避
不純物からなる鋼を連続鋳造して得られる高温鋳
片を、直接もしくは該高温鋳片を保熱工程または
軽加熱工程のいずれかもしくは保熱および軽加熱
の両工程を経たのちに、Ar3点以上の温度で熱間
圧延して得られた熱延鋼帯を冷延後箱焼鈍するこ
とを特徴とする加工用連続鋳造冷延鋼板の製造方
法。1 C0.03~0.07%, Mn0.22~0.35%, Al, N at the coordinate points a, b, c, d, e, f, g, h in Figure 1.
A high-temperature slab obtained by continuous casting of steel containing the range surrounded by , the remainder consisting of iron and unavoidable impurities, is directly or directly subjected to a heat retention process, a light heating process, or a heat retention and Manufacture of continuous casting cold rolled steel sheet for processing, characterized in that the hot rolled steel strip obtained by hot rolling at a temperature of Ar 3 or higher after passing through both steps of light heating is subjected to cold rolling and box annealing. Method.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP19842781A JPS58100629A (en) | 1981-12-11 | 1981-12-11 | Production of continuously cast and cold rolled steel plate for working |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP19842781A JPS58100629A (en) | 1981-12-11 | 1981-12-11 | Production of continuously cast and cold rolled steel plate for working |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS58100629A JPS58100629A (en) | 1983-06-15 |
JPH0217614B2 true JPH0217614B2 (en) | 1990-04-23 |
Family
ID=16390908
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP19842781A Granted JPS58100629A (en) | 1981-12-11 | 1981-12-11 | Production of continuously cast and cold rolled steel plate for working |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS58100629A (en) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS59110722A (en) * | 1982-12-16 | 1984-06-26 | Nippon Kokan Kk <Nkk> | Direct hot rolling of aluminum killed steel |
JPS62287017A (en) * | 1986-06-04 | 1987-12-12 | Nippon Steel Corp | Production of cold rolled steel sheet having excellent deep drawability |
-
1981
- 1981-12-11 JP JP19842781A patent/JPS58100629A/en active Granted
Also Published As
Publication number | Publication date |
---|---|
JPS58100629A (en) | 1983-06-15 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JPH05306430A (en) | Steel sheet for galvanizing and its production | |
EP0050356B1 (en) | Method for producing ferritic stainless steel sheets or strips containing aluminum | |
JPH0768583B2 (en) | High-tensile cold-rolled steel sheet manufacturing method | |
US4420347A (en) | Process for producing an austenitic stainless steel sheet or strip | |
JPH0152450B2 (en) | ||
JPH0217614B2 (en) | ||
JP2512650B2 (en) | Method for producing Cr-Ni type stainless steel thin plate excellent in material and surface quality | |
JPS61133323A (en) | Production of thin steel sheet having excellent formability | |
JPS62161919A (en) | Manufacture of hard sheet steel for can excellent in drawability and minimized in anisotropy | |
JPS61264136A (en) | Manufacture of al killed steel sheet for deep drawing with very low carbon content having reduced in-plane anisotropy | |
JP2825864B2 (en) | Manufacturing method of cold rolled steel sheet with excellent ductility | |
KR910003878B1 (en) | Making process for black plate | |
JPH0125379B2 (en) | ||
JPH0160531B2 (en) | ||
JPH0257128B2 (en) | ||
JPS6153411B2 (en) | ||
JP2980486B2 (en) | Manufacturing method of steel plate for non-aging low earring container | |
JPS59575B2 (en) | Manufacturing method for high-strength cold-rolled steel sheets with excellent formability | |
JPH02197523A (en) | Manufacture of steel sheet for can | |
JPH058257B2 (en) | ||
JPH08311557A (en) | Production of ferritic stainless steel sheet free from ridging | |
JPH05148548A (en) | Production of high-toughness ferritic stainless steel strip | |
JPH01177321A (en) | Manufacture of cold rolled steel sheet excellent in deep drawability | |
JPS6235462B2 (en) | ||
JPH01177322A (en) | Manufacture of cold rolled steel sheet extremely excellent in deep drawability |