JPS6338529A - Manufacture of base material of cold-rolled steel sheet for continuous annealing - Google Patents
Manufacture of base material of cold-rolled steel sheet for continuous annealingInfo
- Publication number
- JPS6338529A JPS6338529A JP18144086A JP18144086A JPS6338529A JP S6338529 A JPS6338529 A JP S6338529A JP 18144086 A JP18144086 A JP 18144086A JP 18144086 A JP18144086 A JP 18144086A JP S6338529 A JPS6338529 A JP S6338529A
- Authority
- JP
- Japan
- Prior art keywords
- slab
- cold
- rolled steel
- steel sheet
- 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.)
- Granted
Links
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 23
- 238000000137 annealing Methods 0.000 title claims abstract description 18
- 239000000463 material Substances 0.000 title claims abstract description 9
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 238000005098 hot rolling Methods 0.000 claims abstract description 22
- 238000010438 heat treatment Methods 0.000 claims abstract description 19
- 238000004804 winding Methods 0.000 claims abstract description 13
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 6
- 239000002184 metal Substances 0.000 claims abstract description 6
- 229910052751 metal Inorganic materials 0.000 claims abstract description 6
- 238000007711 solidification Methods 0.000 claims abstract description 4
- 230000008023 solidification Effects 0.000 claims abstract description 4
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 230000009466 transformation Effects 0.000 claims abstract description 3
- 229910052760 oxygen Inorganic materials 0.000 claims abstract 3
- 238000000034 method Methods 0.000 claims description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 238000001816 cooling Methods 0.000 abstract description 7
- 238000003303 reheating Methods 0.000 description 8
- 239000000047 product Substances 0.000 description 7
- 238000001556 precipitation Methods 0.000 description 6
- 238000002791 soaking Methods 0.000 description 6
- 239000002244 precipitate Substances 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 230000002411 adverse Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000009877 rendering Methods 0.000 description 1
- 238000001226 reprecipitation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
［産業上の利用分野］
本発明は、連続焼鈍用冷延鋼板母材の製造方法に関する
。
更に詳細には、本発明は、熱間圧延工程で高温巻取を行
った場合と同様な良好な深絞り性な有し、かつ、良好な
表面性状を兼備した冷延鋼板製品を製造し得る連続焼鈍
用冷延鋼板の母材の製造方法に関する。
［従来技術］
深絞り用の冷延鋼板は、冷延後深絞りに先立ち焼鈍が行
なわれる。
焼鈍は、従来箱焼鈍が一般的であったが、現在は連続焼
鈍が広く採用されている。その理由は。
冷延鋼板の連続焼鈍は処理時間が短く高強度の製品が得
られるためである。
しかしながら、連続焼鈍した冷延鋼板は成形性、特に深
絞り性が劣る傾向がある。
ところで、従来、連続焼鈍用冷延鋼板の母材の製造方法
としては次の技術が知られている。
すなわち、連続鋳造法により作られたスラブ、あるいは
、鋳造後に分塊鍛造して得られたスラブを３〜ｂ
で冷却して、その後加熱炉にて高温長時間の加熱（１２
００〜１３００℃×１時間）を行ッテから、巻取温度７
００℃以上の高温で巻取を行なって連続熱間圧延する方
法である。
上記技術において７００℃以上の高温で巻取るのは、連
続焼鈍される冷延鋼板において従来の箱焼鈍による冷延
鋼板に匹敵する深絞り性、すなわちγ値を得るためであ
る。すなわち、上記方法においてはスラブの冷却中にＡ
ＩＮが析出しこの析出したＡＩＮは熱間圧延を行なう際
の加熱ソーキング時に再固溶してしまうので、７００℃
という高温巻取によりＡＩＮを粗大析出せしめる０巻取
温度は高いほどＡＩＨの粗大析出が進行し、連続焼鈍に
よりγ値の高い冷延鋼板を得るに望ましいからである。
［発明が解決しようとする問題点］
しかしながら従来の連続焼鈍冷延鋼板の母材の製造方法
には次のような問題点がある。
■従来方法においては、？ｘ続熱間圧延に先立ち１２０
０〜１３００℃の高温に１時間以上の長時間の加熱をス
ラブに施しているが、この加熱量は莫大なものである。
また、１２００〜１３００℃の高温に１時間以上加熱す
ると冷却時に析出したＡＩＮが分解・再固溶してしまい
、後の熱間圧延時に微細に再析出してしまう、この微細
に再析出したＡｉＮは深絞り性を低下せしめる。それを
避けるべく加熱温度を下げると、一旦室温まで冷却され
たスラブでは熱間圧延における仕上温度が低くなってし
まう。
■上記方法では巻取温度が高温であり、巻取温度を高く
すると、表面スケールが生じ、脱炭により粒子の粗大化
（フェライト結晶の粗大化）がおこり、冷延鋼板の外観
を著しく損ねる。これを防止すべく巻取温度を７００”
Ｏ以下に押さえると、連続焼鈍では箱焼鈍で得られる製
品に匹敵するγ値のものは製造できない。
［問題点を解決するための手段］
上記問題点は、
重量％で、
Ｃ；ｏ、ｏｔ〜０．０６％
Ｍ ｒ、 ； ０ 、０２〜０ 、３％Ｓ ；＜ｏ、
ｏｔ％
ｓｏｌ ＡＭ； ０．０１〜０．０６％ｏ ；＜０．
０１％
Ｎ 、＜０．００６％
を含有し、残部鉄及び不可避的不純物から成る連続焼鈍
用冷延鋼板の母材を製造する方法において、溶湯を鋳造
後、該溶湯を凝固せしめることによりスラブを得、凝固
後のスラブが５５０℃以下とならないように該スラブの
温度を保持し、該スラブの温度が１０５０℃未満の場合
には８℃／ｍｉｎ以上の加熱速度で１０５０〜１１８０
℃に加熱を行った後に、該スラブの温度が１０５０℃以
上の場合には加熱を行うことなく熱間圧延を開始し、該
熱間圧延温度をＡｒ３変態点以上で終了し、６５０℃以
下で巻取を行うことを特徴とする連続焼鈍用冷延鋼板の
製造方法によって解決される。
以下に本発明をより詳細に説明する。
（成分限定理由）
Ｃは冷延鋼板製品の強度を得るのに必要な成分である。
特に０．０１％未満では製品の強度が不足するだけでな
く、連続焼鈍後の歪時効劣化が大きいので好ましくない
、また０、０６％を越えると深絞り性が劣化する。従っ
て、Ｃ量は０．０１〜０．０６％に限定した。
Ｍｎ
Ｍｎは、Ｓに起因する熱間脆性を防止する効果を有し、
このため０．０２％以上存在するのが好ましい、しかし
、多量に存在すると、一般に成形性の悪化を招く０本発
明鋼のように、Ｃ量の少ない鋼種では、その弊害は軽微
であるが、再結晶温度を高める点で好ましくない、この
ため０．３％を上限とする。
Ｎは、延び特性値を下げ、従ってプレス加工等における
引張り特性を悪くするので少ない程良く、０．００６％
を上限とする。
Ｓ、（Ｏ）
Ｓ及び[Industrial Application Field] The present invention relates to a method for manufacturing a cold rolled steel plate base material for continuous annealing. More specifically, the present invention can produce a cold rolled steel sheet product that has good deep drawability similar to that obtained when high temperature coiling is performed in a hot rolling process, and also has good surface properties. The present invention relates to a method for manufacturing a base material of a cold-rolled steel plate for continuous annealing. [Prior Art] A cold rolled steel sheet for deep drawing is annealed after cold rolling and prior to deep drawing. Conventionally, box annealing was common, but continuous annealing is now widely used. The reason is. This is because continuous annealing of cold-rolled steel sheets takes a short processing time and produces high-strength products. However, continuously annealed cold rolled steel sheets tend to have poor formability, particularly deep drawability. By the way, the following technique is conventionally known as a method for manufacturing a base material of a cold-rolled steel sheet for continuous annealing. That is, a slab made by a continuous casting method or a slab obtained by blooming forging after casting is cooled at 3 to b, and then heated at a high temperature for a long time in a heating furnace (12
00 to 1300℃ x 1 hour), and the winding temperature was 7.
This method involves continuous hot rolling by winding at a high temperature of 00°C or higher. In the above technique, the reason for winding at a high temperature of 700° C. or higher is to obtain deep drawability, that is, a γ value, comparable to that of a conventional box-annealed cold-rolled steel sheet in a continuously annealed cold-rolled steel sheet. That is, in the above method, A
Since IN precipitates and this precipitated AIN re-dissolves during heating soaking during hot rolling,
This is because the higher the zero coiling temperature at which AIN is coarsely precipitated by high-temperature coiling, the more coarsely AIH is precipitated, which is desirable for obtaining a cold-rolled steel sheet with a high γ value through continuous annealing. [Problems to be Solved by the Invention] However, the conventional method for manufacturing a base material of a continuously annealed cold rolled steel sheet has the following problems. ■In the conventional method? x prior to continued hot rolling 120
The slab is heated to a high temperature of 0 to 1,300°C for a long time of one hour or more, and the amount of heating is enormous. In addition, when heated to a high temperature of 1200 to 1300°C for more than 1 hour, the AIN that precipitates during cooling decomposes and re-dissolves into a solid solution, and then finely re-precipitated during hot rolling. reduces deep drawability. If the heating temperature is lowered to avoid this, the finishing temperature during hot rolling will be lower for the slab once cooled to room temperature. (2) In the above method, the coiling temperature is high, and when the coiling temperature is increased, surface scale is generated, and decarburization causes coarsening of particles (coarseling of ferrite crystals), which significantly impairs the appearance of the cold-rolled steel sheet. To prevent this, the winding temperature was set to 700".
If the value is kept below O, continuous annealing cannot produce products with a γ value comparable to products obtained by box annealing. [Means for solving the problems] The above problems are as follows: In weight%, C; o, ot ~ 0.06% Mr, ; 0, 02~0, 3% S; < o,
ot% sol AM; 0.01-0.06%o;<0.
01% N, <0.006%, and the remainder is iron and unavoidable impurities. In this method, a slab is formed by casting a molten metal and then solidifying the molten metal. The temperature of the slab after solidification is maintained so that it does not fall below 550°C, and if the temperature of the slab is below 1050°C, it is heated at a heating rate of 8°C/min or higher to 1050 to 1180°C.
After heating to ℃, if the temperature of the slab is 1050℃ or higher, hot rolling is started without heating, and the hot rolling temperature is finished at the Ar3 transformation point or higher and is lower than 650℃. The problem is solved by a method for manufacturing a cold-rolled steel sheet for continuous annealing, which is characterized by winding. The present invention will be explained in more detail below. (Reasons for limiting ingredients) C is a component necessary to obtain the strength of cold-rolled steel sheet products. In particular, if it is less than 0.01%, not only the strength of the product will be insufficient, but also the strain aging after continuous annealing will be large, which is undesirable, and if it exceeds 0.06%, deep drawability will deteriorate. Therefore, the amount of C was limited to 0.01 to 0.06%. Mn Mn has the effect of preventing hot embrittlement caused by S,
For this reason, it is preferable that the amount of carbon is present in an amount of 0.02% or more. However, if it is present in a large amount, the formability generally deteriorates. In steel types with a small amount of carbon, such as the steel of the present invention, the adverse effects are minor, but It is undesirable because it increases the recrystallization temperature, so the upper limit is set at 0.3%. N lowers the elongation property value and therefore worsens the tensile properties in press working, etc., so the smaller the better, 0.006%
is the upper limit. S, (O) S and
〔０〕は、いずれも存在量が少ない程成形性も改
善される。このため、Ｓは０．０１％、For [0], the smaller the amount present, the better the moldability is. Therefore, S is 0.01%,
〔０〕は０．０
１％を許容上限とし、いずれも少ない程、好ましい。
ｏｌＡｉ
ｓａｌＡ又は、鋼溶製時の脱酸剤としての役割を有する
ほか、前記ＮをＡｉＮとして固定・無害化するのに有効
である。このため、０．０１％以上加えられる。しかし
、あまり多くなると、効果が飽和するだしすでなく、非
金属介在物の増加による表面性状の悪化、あるいは再結
晶粒の微細化を招き好ましくない、このため０．０６％
を上限とする。
なお、脱酸及び鋳造性確保のためＳｉを含有せしめるが
、この場合上限を０．０５％とする。
０．０５％を越えると表面酸化スケール状態の悪化をま
ねく。
また１本発明では、凝固後のスラブが５５０℃以下トナ
らないようにスラブの温度を保持する。
スラブ溶製後、該スラブを５５０℃以上に保持するのは
以下のような理由による０本発明は、熱延後のフェライ
ト域で析出する有害な微細析出物を防止するため、熱延
前の加熱時にＡ丈Ｎ等を析出させようとするものである
。５５０℃以下に冷却すると、スラブ冷却過程でこれら
の析出が起こってしまい、再加熱ソーキング中には分解
、再固溶が生じ、熱延後、微細に再析出する。これに対
して冷却温度を５５０℃以上とすることにより、スラブ
冷却中にはＡｆＬＮ等が析出せず、過飽和状態となる。
冷却後１本発明では、１０５０〜１１８０℃以上の温度
で熱間圧延を開始する。スラブが１０５０℃以上の場合
はそのまま熱間圧延を開始すればよ＜、１ｏｓｏ℃未渦
の場合には８℃／ｍｉｎ以上の加熱速度で１０５０〜１
１８０℃に再加熱−ソーキングしてから熱間圧延を開始
する。
この８℃／ ｍ ｉ ｎ以上の再加熱により熱間圧延時
あるいは再加熱・ソーキング時に過飽和状態は解除され
Ａｔ；ＬＮが析出する。
スラブを５５０℃以下に冷却せず、かつ、１０５０℃以
下の場合は８℃／ｍｉｎ以上の加熱速度で１０５０〜１
１８０℃に再加熱して熱間圧延することによりソーキン
グ中のＡ見Ｎの析出がかえって促進されることが判った
。メカニズムは必ずしも明らかではないが、かかる加熱
速度により加熱することによりスラブ冷却中にはＡＪＬ
Ｎの析出が進行せず、過飽和にＡＩＮが固溶しているた
め、ソーキング過程での析出の駆動力となり。
かえってＡＩＮが析出すると考えられる。
本発明においては６５０℃以下で巻取を行う。
連続焼鈍冷延鋼板が従来工程で優れた深絞り性を得るた
めには７００℃以上で巻取る必要があることは前述した
とおりである。これはかかる高温の巻取過程でＡｕＮの
粗大析出を起こさせるためであることも前述したとおり
である。それに対し本発明では巻取前の工程でこれを成
しているため、巻取工程で析出させる必要はない、従っ
て、６５０℃以下という低温で巻取ることが可能である
。その結果スケール量の低減、形状向上をもたらす、逆
に、６５０℃以上で巻取ると、熱延粒径が異常成長して
γ値の劣化をもたらす。
［発明の実施例］
表に示す組成鋼を溶製した。
ＡｉＮＡ３．Ｂｌ〜Ｂ３．Ｃ１〜Ｃ３はそれぞれ同じ組
成をもつものである。Ｃｌ−Ｃ５はＣ擾が本発明範囲よ
り多い比較例である。
ＡＩ 、Ａ２ 、Ｂｌ 、Ｂ２．Ｃ１、Ｃ２はいずれも
凝固後５５０℃以上に保持した。一方、Ａ３゜Ｂ３ 、
Ｃ３は室温まで一旦冷却した比較例である。
Ａｔ 、Ａ２．Ｂｌ 、Ｂ２．Ｃ１、Ｃ２のうちＢ２を
除きいずれも１０５０℃以下であったので１０５０〜１
１８０℃の範囲に再加熱を行なった。再加熱の加熱速度
はいずれも８℃／ｍｉｎ以上である。
Ｂ２は１０５０℃以上であったのでそのまま再加熱する
ことなく熱間圧延を行なった。
巻取温度はＣ２を除きいずれも６５０℃以下である。Ｃ
２は７００℃で行なった。
これらの熱間圧延条件は表に併記した。
熱延後、７５％の冷間圧延を行った後、７２０”ＯＸＩ
、５ｍ１ｎ〜４００℃Ｘ３ｍ１ｎの連続焼鈍を行った。
さらに、０．６％のスキンパス後、機械的性質を調査し
た。
表より１本発明の範囲内の条件で製造された冷延鋼板（
ＡＩ、Ａ２．Ｂｌ、Ｂ２）はいずれも深絞り成形性、す
なわち、γ値、Ｅｌが飛躍的に向上している上、加熱炉
原単位の低減が図られているのが明らかである。従って
、この発明によれば深絞り性の優れた冷延鋼板を安価に
製造できる。
［発明の効果］
本発明によれば上述の従来技術の問題点を解決し、深絞
り性の優れた冷延鋼板製品を与え得る連続焼鈍用の冷延
母材の製造方法を提供することができる。
手続補正書
昭和６１年 ９月 ９日[0] is 0.0
The permissible upper limit is 1%, and the lower the content, the better. In addition to having a role as a deoxidizing agent during steel melting, it is effective in fixing and rendering harmless the N as AiN. For this reason, 0.01% or more is added. However, if the amount is too large, the effect will not be saturated, and it will not only lead to deterioration of the surface quality due to an increase in nonmetallic inclusions, but also to the refinement of recrystallized grains, which is not desirable.For this reason, 0.06%
is the upper limit. Note that Si is included to ensure deoxidation and castability, but in this case the upper limit is set to 0.05%. If it exceeds 0.05%, the condition of the surface oxide scale will deteriorate. Further, in the present invention, the temperature of the solidified slab is maintained so that it does not exceed 550°C. The reason for maintaining the slab at 550°C or higher after melting the slab is as follows. In the present invention, in order to prevent harmful fine precipitates that precipitate in the ferrite region after hot rolling, The purpose is to precipitate A length N etc. during heating. If the slab is cooled to 550° C. or below, precipitation will occur during the slab cooling process, decomposition and solid solution will occur during reheating and soaking, and fine reprecipitation will occur after hot rolling. On the other hand, by setting the cooling temperature to 550° C. or higher, AfLN etc. do not precipitate during slab cooling, resulting in a supersaturated state. After cooling 1. In the present invention, hot rolling is started at a temperature of 1050 to 1180°C or higher. If the temperature of the slab is 1050℃ or higher, just start hot rolling.
After reheating and soaking to 180°C, hot rolling is started. By this reheating at 8° C./min or more, the supersaturated state is released during hot rolling or during reheating/soaking, and At; LN is precipitated. If the slab is not cooled to 550℃ or lower, and the temperature is 1050℃ or lower, the heating rate is 8℃/min or higher to 1050~1
It was found that reheating to 180° C. and hot rolling actually promoted the precipitation of A-N during soaking. Although the mechanism is not necessarily clear, heating at such a heating rate reduces AJL during slab cooling.
Since N precipitation does not proceed and AIN is dissolved in supersaturated form, it becomes the driving force for precipitation during the soaking process. It is considered that AIN is instead precipitated. In the present invention, winding is performed at 650° C. or lower. As mentioned above, in order to obtain excellent deep drawability of a continuously annealed cold-rolled steel sheet in the conventional process, it is necessary to coil the sheet at a temperature of 700° C. or higher. As mentioned above, this is because coarse precipitation of AuN occurs during the high-temperature winding process. In contrast, in the present invention, this is accomplished in a step before winding, so there is no need for precipitation in the winding step, and therefore it is possible to wind at a low temperature of 650° C. or lower. As a result, the amount of scale is reduced and the shape is improved. On the other hand, when the steel is rolled at a temperature of 650° C. or higher, the hot-rolled grain size grows abnormally, resulting in a deterioration of the γ value. [Examples of the Invention] Steels with compositions shown in the table were melted. AiNA3. Bl~B3. C1 to C3 each have the same composition. Cl-C5 is a comparative example in which the C content is higher than the range of the present invention. AI, A2, Bl, B2. Both C1 and C2 were maintained at 550° C. or higher after solidification. On the other hand, A3°B3,
C3 is a comparative example in which the sample was once cooled to room temperature. At, A2. Bl, B2. Among C1 and C2, all except B2 were below 1050℃, so 1050~1
Reheating was performed to a range of 180°C. The heating rate for reheating is 8° C./min or higher in all cases. Since the temperature of B2 was 1050° C. or higher, hot rolling was performed without reheating. The winding temperature is 650° C. or lower in all cases except C2. C
2 was carried out at 700°C. These hot rolling conditions are also listed in the table. After hot rolling and 75% cold rolling, 720”OXI
, 5 m1n to 400°C x 3 m1n continuous annealing was performed. Furthermore, the mechanical properties were investigated after a 0.6% skin pass. From the table, 1 cold rolled steel sheet manufactured under conditions within the scope of the present invention (
AI, A2. It is clear that both Bl and B2) have dramatically improved deep drawing formability, that is, the γ value and El, and have also achieved a reduction in heating furnace consumption. Therefore, according to the present invention, a cold rolled steel sheet with excellent deep drawability can be manufactured at low cost. [Effects of the Invention] According to the present invention, it is possible to provide a method for manufacturing a cold rolled base material for continuous annealing, which solves the problems of the prior art described above and can provide a cold rolled steel sheet product with excellent deep drawability. can. Procedural amendment September 9, 1986
Claims (1)
用冷延鋼板の母材を製造する方法において、溶湯を鋳造
後、該溶湯を凝固せしめることによりスラブを得、凝固
後のスラブが５５０℃以下とならないように該スラブの
温度を保持し、該スラブの温度が１０５０℃未満の場合
には８℃／ｍｉｎ以上の加熱速度で１０５０〜１１８０
℃に加熱を行った後に、該スラブの温度が１０５０℃以
上の場合には加熱を行うことなく熱間圧延を開始し、該
熱間圧延温度をＡｒ＿３変態点以上で終了し、６５０℃
以下で巻取を行うことを特徴とする連続焼鈍用冷延鋼板
の製造方法。[Claims] In weight %, C; 0.01-0.06% Mn; 0.02-0.3% S; <0.01% solAl; 0.01-0.06% O; < In a method for producing a base material for continuous annealing cold-rolled steel sheet containing 0.01% N; 0.006% and the balance consisting of iron and unavoidable impurities, a slab is formed by casting a molten metal and then solidifying the molten metal. The temperature of the slab after solidification is maintained so that it does not fall below 550°C, and if the temperature of the slab is below 1050°C, it is heated to 1050 to 1180°C at a heating rate of 8°C/min or more.
After heating to ℃, if the temperature of the slab is 1050℃ or higher, hot rolling is started without heating, the hot rolling temperature is finished at Ar_3 transformation point or higher, and 650℃.
A method for manufacturing a cold-rolled steel sheet for continuous annealing, characterized in that winding is performed as follows.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61181440A JPH0765112B2 (en) | 1986-07-31 | 1986-07-31 | Method for manufacturing base material of cold rolled steel sheet for continuous annealing |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61181440A JPH0765112B2 (en) | 1986-07-31 | 1986-07-31 | Method for manufacturing base material of cold rolled steel sheet for continuous annealing |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6338529A true JPS6338529A (en) | 1988-02-19 |
| JPH0765112B2 JPH0765112B2 (en) | 1995-07-12 |
Family
ID=16100807
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61181440A Expired - Fee Related JPH0765112B2 (en) | 1986-07-31 | 1986-07-31 | Method for manufacturing base material of cold rolled steel sheet for continuous annealing |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0765112B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0480345A (en) * | 1990-07-19 | 1992-03-13 | Nippon Steel Corp | Cold rolled steel sheet excellent in workability, roughening property and earing property and its manufacture |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60162731A (en) * | 1984-01-31 | 1985-08-24 | Nippon Steel Corp | Production of continuously annealed and cold rolled steel sheet having small ageability |
| JPS60228617A (en) * | 1984-04-25 | 1985-11-13 | Nippon Steel Corp | Manufacture of nonaging cold rolled steel plate by continuous casting and continuous annealing method |
-
1986
- 1986-07-31 JP JP61181440A patent/JPH0765112B2/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60162731A (en) * | 1984-01-31 | 1985-08-24 | Nippon Steel Corp | Production of continuously annealed and cold rolled steel sheet having small ageability |
| JPS60228617A (en) * | 1984-04-25 | 1985-11-13 | Nippon Steel Corp | Manufacture of nonaging cold rolled steel plate by continuous casting and continuous annealing method |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0480345A (en) * | 1990-07-19 | 1992-03-13 | Nippon Steel Corp | Cold rolled steel sheet excellent in workability, roughening property and earing property and its manufacture |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0765112B2 (en) | 1995-07-12 |
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