JPS593527B2 - Manufacturing method of cold-rolled steel sheet for deep drawing with excellent formability - Google Patents
Manufacturing method of cold-rolled steel sheet for deep drawing with excellent formabilityInfo
- Publication number
- JPS593527B2 JPS593527B2 JP55094336A JP9433680A JPS593527B2 JP S593527 B2 JPS593527 B2 JP S593527B2 JP 55094336 A JP55094336 A JP 55094336A JP 9433680 A JP9433680 A JP 9433680A JP S593527 B2 JPS593527 B2 JP S593527B2
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- temperature
- cold
- annealing
- temperature range
- recrystallization
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- 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)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
【発明の詳細な説明】
この発明は、成形性のすぐれた深絞り用冷延鋼板の製造
法に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing a cold-rolled steel sheet for deep drawing with excellent formability.
冷延鋼板の製造法は、周知のごとく、熱間圧延機で圧延
した銅帯をダウンコイラで巻取った後、酸洗→冷間圧延
→表面清浄→焼なまし・・・・・・の各処理工程を経て
冷延鋼板を製造しているが、その材質としては近年リム
ド鋼に変って、アルミギルド鋼が使用されるようになっ
てきた。As is well known, the manufacturing method for cold-rolled steel sheets involves the steps of pickling, cold rolling, surface cleaning, annealing, etc. after rolling a copper strip in a hot rolling mill and winding it up in a down coiler. Cold-rolled steel sheets are manufactured through a processing process, and in recent years the material used has changed from rimmed steel to aluminum guild steel.
これは、高強度鋼であると共に成分偏析にもとづくコイ
ル内の特性変動が少なく、しかも時効劣化し難い特徴を
有するのみならず、バッチ式焼なまし法ではその材質中
に固溶している窒素を焼なまし処理工程中に微細なＡｔ
Ｎとして析出させて成形性（深絞り性）の指数として用
いられるランクフォード値（以下下値と称す）を非常に
高いレベルに持ちきたすことができるためである。This is not only a high-strength steel with little variation in properties within the coil due to component segregation and resistance to aging deterioration, but also has the advantage of not only being a high-strength steel, but also having the characteristics of being resistant to aging deterioration. During the annealing process, fine At
This is because it is possible to bring the Lankford value (hereinafter referred to as the lower value), which is used as an index of formability (deep drawability), to a very high level by precipitating it as N.
ところが、連続炉なまし法においては、このアルミキル
ド鋼の特徴であるところの微細なＡｔＮの析出による７
値の向上が一般的に難しい。However, in the continuous furnace annealing method, 7
It is generally difficult to improve the value.
これは昇熱速度が速いため、微細ＡｔＮの析出後、再結
晶が進行するという順序が逆又はこれに近い状態になる
ことによる。This is because the heating rate is fast, so that the order in which recrystallization proceeds after the precipitation of fine AtN is reversed or in a state similar to this.
これは、連続炉なまし法において、ＡｔＮとしての析出
効果が全く得られない上に、再結晶粒成長をも阻害して
いるためである。This is because, in the continuous furnace annealing method, not only no precipitation effect as AtN is obtained, but also recrystallized grain growth is inhibited.
そこで、連続炉なまし法における、この７値の向上につ
いては近年、下記に示すような方法が提案されている。Therefore, in recent years, the following methods have been proposed to improve these seven values in the continuous furnace annealing method.
１ ダウンコイラでの巻取りを、高温巻取りとすること
により、炭化物の凝集及びＡｔＮの大型析出物の析出を
施し、７値の向上と再結晶粒成長を図ったもの。1. High-temperature winding with a down coiler results in the agglomeration of carbides and the precipitation of large AtN precipitates, improving the 7 value and increasing recrystallized grain growth.
２ 連続炉での再結高炉なまし温度を通常より昇温させ
、その鋼板の組織をフェライト＋オーステナイト領域ま
で昇温して集合組織の改善を図り、下値の向上を目指し
たもの。2. Reconsolidation in a continuous furnace The blast furnace annealing temperature is raised above normal, and the temperature of the steel sheet is raised to the ferrite + austenite region to improve the texture and improve the bottom value.
３ チタンを添加することにより下値の向上を図ったも
のがある。3. There are some products in which the lower value has been improved by adding titanium.
しかし、上記１の高温巻取りを行うと、脱スケ−ル性や
表面性状の悪化、結晶粒の粗大化、形状不良などが生じ
、冷延母材としては格落ちする場合が多くなる。However, when the above-mentioned high-temperature winding is carried out in 1, descaling properties and surface properties are deteriorated, crystal grains are coarsened, and the shape is defective, etc., and the quality of the material is often degraded as a cold-rolled base material.
又、２の再結重焼なまし温度を上げると、連続炉に要す
る燃料原単位が増大し、能率の低下をきたすと共にコス
トアップとなる。Furthermore, if the temperature of the reconsolidation double annealing in step 2 is increased, the fuel consumption rate required for the continuous furnace increases, resulting in a decrease in efficiency and an increase in cost.
又、３のチタンを添加すると、チタンは炭素と結合する
ため、チタンの添加時はその際に真空脱炭処理も施さね
ばならず、その処理とチタンの使用により、コストアッ
プとなるなどの欠点があった。In addition, when titanium is added in step 3, titanium combines with carbon, so when adding titanium, a vacuum decarburization treatment must be performed at that time, and this treatment and the use of titanium increase costs. was there.
この発明は、これらの方法をとらず、連続炉なまし過程
でのヒートパターンを一部変えることにより、上記の欠
点を解消し得る成形性のすぐれた深絞り用冷延鋼板の製
造法を提案するものである。This invention proposes a method for manufacturing cold-rolled steel sheets for deep drawing with excellent formability, which eliminates the above-mentioned drawbacks by partially changing the heat pattern during the continuous furnace annealing process, without using these methods. It is something to do.
すなわち、この発明は炭素０．１０％以下、けい素０．
２０係以下、マンガン０．１０〜０．４０％、りん０．
０３％以下、アルミニウム０．０２〜０．１５係、窒素
０．００２５〜０．０２％、残部実質的に鉄よりなる鋼
を、通常の熱間圧延を施して６００℃以下３００℃以上
でコイルに巻取り、酸洗後圧工率４０係以上８０係以下
で冷間圧延を行った後、３５０℃以上再結晶温度以下好
ましくは４５０〜５５０℃の温度域に１０〜６０秒予熱
保持し、引続き再結晶温度以上８００℃以下の温度域に
短時間保持して再結重焼なましを行い、次いで２５０〜
４５０℃の温度域に降温して過時効処理を施すか、又は
２００℃以下に急冷した後、再加熱して２５０〜４５０
℃の温度域で過時効処理を施すことを要旨とするもので
ある。That is, this invention has carbon content of 0.10% or less and silicon content of 0.10% or less.
20 or less, manganese 0.10-0.40%, phosphorus 0.
0.3% or less, aluminum 0.02 to 0.15%, nitrogen 0.0025 to 0.02%, and the balance substantially iron, is subjected to normal hot rolling to form a coil at a temperature of 600°C or lower and 300°C or higher. After pickling and cold rolling at a rolling ratio of 40 to 80, preheat and hold for 10 to 60 seconds at a temperature range of 350°C or higher and below the recrystallization temperature, preferably 450 to 550°C, Subsequently, recrystallization heavy annealing is performed by holding for a short time in a temperature range above the recrystallization temperature and below 800°C, and then at 250 - 800°C.
Either the temperature is lowered to a temperature range of 450℃ and an overaging treatment is performed, or the temperature is rapidly cooled to 200℃ or less and then reheated to a temperature of 250 to 450℃.
The gist of this is to perform overaging treatment in the temperature range of ℃.
以下、この発明について詳細に説明する。This invention will be explained in detail below.
第１図、第２図及び第３図に示すように、１ａ、２ａ及
び３ａはこの発明法の再結重焼なまし過程におけるヒー
トパターンの曲線を示し、１ｂ、２ｂ及び３ｂは従来法
の再結重焼なまし過程におけるヒートパターンの曲線を
示すもので、連続炉においてコイルを連続的に巻き戻し
、銅帯の状態で焼なまし炉の中を通過させながら連続炉
なましを行うが、抽入された銅帯をいったん３５０℃以
上〜再結晶温度以下の温度範囲である焼なまし予熱温度
域（ＰｒｅＲＡ）で１０〜６０秒程度の短時間予熱保持
する。As shown in FIGS. 1, 2, and 3, 1a, 2a, and 3a show the heat pattern curves in the reconsolidation double annealing process of the present method, and 1b, 2b, and 3b show the curves of the conventional method. This shows the heat pattern curve during the reconsolidation heavy annealing process, in which the coil is continuously unwound in a continuous furnace and the copper strip is passed through the annealing furnace for continuous furnace annealing. The injected copper strip is once preheated for a short period of about 10 to 60 seconds in the annealing preheating temperature range (PreRA), which is a temperature range of 350° C. or higher and below the recrystallization temperature.
この焼なまし予熱温度域（ＰｒｅＲＡ）を施すことによ
シ、冷延鋼板中の窒素ＮをＡｔＮとして微細に析出する
ようにしたものである。By applying this annealing preheating temperature range (PreRA), nitrogen N in the cold rolled steel sheet is finely precipitated as AtN.
すなわち、アルミキルド鋼は冷延後の再結重焼なまし初
期段階においてＡｔＮを微細に析出させやすく、これに
より再結晶集合組織を改善し、高７値の得られることが
知られている。That is, it is known that in aluminum killed steel, AtN is easily precipitated finely in the initial stage of recrystallization heavy annealing after cold rolling, and this improves the recrystallization texture and provides a high 7 value.
そこで、発明者は連続炉なまし法において、ＡｔＮの析
出しやすい温度域に短時間保持することにより、Ａバを
十分析出させて集合組織を改善し、下値を向上せしめ、
成形性の向上を図るものである。Therefore, in the continuous furnace annealing method, the inventors maintained the temperature in a temperature range where AtN is easy to precipitate for a short time, thereby allowing a sufficient amount of A to be extracted, improving the texture, and improving the lower value.
The purpose is to improve moldability.
そして、その後の温度過程は通常のヒートパターンと同
様の熱処理を施す。Then, the subsequent temperature process is performed in the same manner as in a normal heat pattern.
すなわち、Ａ１変態点近傍の再結重焼なまし温度域ＲＡ
（温度は後述する）まで昇温して２０〜１２０秒程度保
持し、この間に再結晶、粒成長の過程を経て軟化させ、
成形加工性を向上させるものである。That is, the recrystallization heavy annealing temperature range RA near the A1 transformation point
(The temperature will be described later) and held for about 20 to 120 seconds, during which it softens through the process of recrystallization and grain growth.
This improves moldability.
次いで、２５０〜４５０℃の過時効処理温度域ＯＡまで
降温、又は２００℃以下に急冷後再加熱して２５０〜４
５０℃の温度で２〜４分間保持し、時効の発生原因とな
る固溶炭素を減少させる方法である。Next, the temperature is lowered to the overaging treatment temperature range OA of 250 to 450°C, or rapidly cooled to 200°C or less and then reheated to 250 to 450°C.
This is a method of holding at a temperature of 50° C. for 2 to 4 minutes to reduce solid solution carbon, which causes aging.
又、過時効処理においては、設備の都合上バッチ炉で過
時効処理を行ういわゆるボストアニール法であっても基
本的にはなんら差異がないため、ボストアニールを適用
してもよい。Further, in the over-aging treatment, even if the over-aging treatment is carried out in a batch furnace due to the equipment, there is basically no difference in the so-called Bosto annealing method, and therefore Bosto annealing may be applied.
すなわち、第３図に示すよ・うに、再結重焼なまし温度
域ＲＡから急冷した後、バッチ式加熱炉を用いて２５０
〜４５０℃の過時効処理温度域ＯＡに再加熱し、コール
ドスポット（最冷点）において３０分以上保持するもの
である。That is, as shown in FIG.
It is reheated to the overaging treatment temperature range OA of ~450°C and held at the cold spot (the coldest point) for 30 minutes or more.
上記焼なまし予熱温度域（ＰｒｅＲＡ）を３５０℃以上
〜再結晶温度以下としたのは、３５０℃未満ではＡ７Ｎ
の析出に必要な熱量が得られず、又再結晶温度を越える
とこの発明の目的とする微細ＡｔＮの析出後再結晶させ
、集合組織を改善するのが困難となるからである。The above annealing preheating temperature range (PreRA) was set from 350℃ or higher to the recrystallization temperature or lower because A7N was set below 350℃.
This is because the amount of heat required for precipitation cannot be obtained, and if the temperature exceeds the recrystallization temperature, it becomes difficult to recrystallize fine AtN after precipitation and improve the texture, which is the object of the present invention.
したがって、ＡｔＮを効率的に析出させるため焼なまし
予熱温度（ＰｒｅＲＡ）は４５０〜５５０℃が好ましく
、又その時間は１０秒以上保持すれば十分ＡｔＮを析出
させることができる。Therefore, in order to efficiently precipitate AtN, the annealing preheating temperature (PreRA) is preferably 450 to 550°C, and if the temperature is maintained for 10 seconds or more, AtN can be sufficiently precipitated.
なお、このＡｔＨの析出時間は長いほど好ましいが、設
備長さの増大につながることから、実質的には６０秒ぐ
らいが上限となる。The longer the AtH precipitation time is, the more preferable it is, but since this leads to an increase in the length of the equipment, the practical upper limit is about 60 seconds.
上記再結重焼なまし温度域ＲＡは、再結晶温度以上８０
０℃以下、又は通常と同じ７００〜８５０ ’Ｃの範囲
のいずれでもよいが、炉の燃料原単位を考慮してできる
だけ低い方がよい。The above recrystallization annealing temperature range RA is 80° above the recrystallization temperature.
The temperature may be 0° C. or lower, or the same range of 700 to 850° C., but it is better to keep it as low as possible considering the fuel consumption of the furnace.
この点に関し、後述する下値の向上により、再結晶温度
以上〜８５０℃以下で再結重焼なましが可能となり、好
ましくは６５０〜７５０℃がよい。In this regard, due to the improvement in the lower value described below, recrystallization double annealing becomes possible at a temperature above the recrystallization temperature and below 850°C, preferably between 650 and 750°C.
又、その保持時間は長い方がよいが、設備上許容範囲内
の２０〜１２０秒程度で十分再結重焼なまし処理効果が
得られる。Further, although the longer the holding time is, the longer the holding time is, the longer the holding time is, but the effect of recrystallization heavy annealing treatment can be sufficiently obtained with a holding time of about 20 to 120 seconds, which is within the allowable range in terms of equipment.
又、過時効処理温度ＯＡは、通常と同じ２５０〜４５０
℃の時効処理に適した温度範囲でよく、その時間も同じ
く通常の２〜４分の時効処理時間で十分である。In addition, the overaging treatment temperature OA is 250 to 450, which is the same as usual.
The temperature range suitable for aging treatment of .degree. C. may be used, and the usual aging treatment time of 2 to 4 minutes is sufficient.
上記炉内における焼な甘しの予熱操作は、炉内の温度調
整を行うことにより容易にこの発明の焼なまし予熱過程
を設けることができる。The above-mentioned preheating operation for annealing and sweetening in the furnace can be easily performed as the annealing and preheating process of the present invention by adjusting the temperature inside the furnace.
このように、再結高燐なまし時のヒートパターンを一部
変えるのみで、成品の７値が向上し、成形性がすぐれ、
ひずみ時効の発生を抑制した高品質の成品を製造するこ
とができる。In this way, by only partially changing the heat pattern during reconsolidation high phosphorus annealing, the 7 value of the finished product can be improved, the formability is excellent,
It is possible to produce high-quality products that suppress the occurrence of strain aging.
このＴ値の向上に伴い、下記に示す種々の問題も解消さ
れる。With this improvement in T value, various problems described below are also solved.
すなわち、ダウンコイラでの７５０℃程度の高温巻取り
を要せず、コイルの巻取温度を６６０℃以下にしても確
実に７値の向上を図ることができる。That is, it is not necessary to wind the coil at a high temperature of about 750° C. in a down coiler, and even if the coil winding temperature is set to 660° C. or lower, it is possible to reliably improve the value of 7.
したがって、高温巻取りにより生じる脱スケール性、表
面性状の悪化や結晶粒の粗大化、形状不良などを抑制す
ることができ、最適なる冷延母材を得ることができる。Therefore, it is possible to suppress descaling properties, deterioration of surface properties, coarsening of crystal grains, poor shape, etc. caused by high-temperature winding, and it is possible to obtain an optimal cold-rolled base material.
又、再結高燐なまし温度域ＲＡば、通常集合組織の改善
を図って７値を向上し得るように、短時間内に７００〜
８５０℃まで昇温しでいるが、この発明法においては予
熱段階を新たに設けて７値を向上し得るものであるから
、再結高燐なまし温度域ＲＡを６５０〜７５０℃程度ま
で下げることができる。In addition, in the reconsolidation high phosphorus annealing temperature range RA, it is possible to improve the normal texture and improve the 7 value within a short period of time.
Although the temperature is raised to 850℃, in this invention method, a new preheating stage is provided to improve the 7 value, so the recondensation high phosphorus annealing temperature range RA can be lowered to about 650 to 750℃. be able to.
このため、連続炉における燃料原単位を確実に低減でき
る。Therefore, the fuel consumption rate in the continuous reactor can be reliably reduced.
又、チタンの添加や真空脱炭処理なども要せず、きわめ
て簡単かつ的確に７値の向上を得ることができる。Moreover, there is no need for addition of titanium or vacuum decarburization, and it is possible to obtain an improvement in the value of 7 very simply and accurately.
又、この発明の冷延鋼板は、例えば連続鋳造法又は造塊
法により製造したアルミキルド鋼冷延鋼板が対象となる
。Further, the cold-rolled steel sheet of the present invention is an aluminium-killed cold-rolled steel sheet manufactured by, for example, a continuous casting method or an ingot-forming method.
この発明において、鋼の化学成分を限定したのは次の理
由による。In this invention, the chemical composition of the steel is limited for the following reason.
炭素は、絞り性を向上させるため低い方が望ましく、炭
素が０．１０％を越えると強度上昇に伴なう延性の低下
及び粗粒化による絞り性延性の劣化が著しくなるため、
０．１０％以下とした。It is desirable that the carbon content be low in order to improve drawability, and if the carbon content exceeds 0.10%, the decrease in ductility due to the increase in strength and the deterioration in drawability due to grain coarsening will become significant.
It was set to 0.10% or less.
けい素は、０．２０％を越えると、鋼板表面に焼なまし
時に着色し、又スケールによる表面欠陥となるため０．
２０％以下がよい。If silicon exceeds 0.20%, the surface of the steel sheet will be colored during annealing, and surface defects due to scale will occur.
20% or less is preferable.
マンカンは、絞り性を向上させるため低い方が望ましい
が、０．１０％未満では赤熱脆性の危険があり、又製造
も困難である。It is desirable that the amount of Manquan is lower in order to improve drawability, but if it is less than 0.10%, there is a risk of red heat brittleness and production is also difficult.
０．４０％を越えると、再結晶集合組織が劣化し、絞り
性の著しい低下をきたすので、マンガンは０１１０〜０
．４０％が好ましい。If it exceeds 0.40%, the recrystallized texture deteriorates and the drawability is significantly reduced.
．． 40% is preferred.
りんは、０．０３％を越えると、その固溶強化により延
性が低下するので、０．０３％以下とする。When phosphorus exceeds 0.03%, ductility decreases due to solid solution strengthening, so the content is set to 0.03% or less.
アルミニウムは、ＡｔＮの析出に必要で、０．０２％未
満では効果が少なく、０．１５％を越えるとスラブ加熱
時のＡＡＮの固溶化が不完全となり、再結晶粒の微細化
により延性が低下するため、０．０２〜０．１５係とし
た。Aluminum is necessary for the precipitation of AtN, and if it is less than 0.02%, it will have little effect, and if it exceeds 0.15%, the solid solution of AAN will be incomplete during slab heating, and the ductility will decrease due to the refinement of recrystallized grains. Therefore, the ratio was set at 0.02 to 0.15.
窒素は、伸びを向上させるためには少ない方がよいが、
０．００２５％未満ではＡ／ＩＩ、Ｈの析出が不十分で
あり、０．０２％を越えると伸びが低下し、アルミニウ
ムと相俟ってスラブ加熱時のＡｔＮの固溶化が不完全と
なるため、０．００２５〜０．０２％としだ。It is better to have less nitrogen in order to improve elongation, but
If it is less than 0.0025%, the precipitation of A/II and H will be insufficient, and if it exceeds 0.02%, the elongation will decrease, and together with aluminum, the solid solution of AtN will be incomplete when heating the slab. Therefore, it is 0.0025 to 0.02%.
又、熱間仕上圧延後の巻取温度を６００℃以下３００℃
以上としたのは、６００°Ｃを越えると巻取後の冷却中
に大型のＡｔＮが析出してしまい、本来の目的であると
ころのＰｒｅＲＡでの微細なＡｔＮの析出が不可能とな
り、３００℃以下では巻取時の銅帯強度が高く、巻取が
困難となり製造上の不具合を生じたり、水冷却のだめの
水量を増大または能率の低下をきたすとともに、３００
℃以下としても絞り性向上に対する効果は変らないから
である。In addition, the coiling temperature after hot finish rolling should be 600℃ or less and 300℃.
The reason for this is that if the temperature exceeds 600°C, large AtN will precipitate during cooling after coiling, making it impossible to precipitate fine AtN in PreRA, which is the original purpose. Below 300 ml, the strength of the copper strip during winding is high, making it difficult to wind and causing manufacturing defects, increasing the amount of water in the water cooling tank, and reducing efficiency.
This is because the effect on improving drawability remains unchanged even if the temperature is below °C.
又、酸洗して表面を脱スケール処理した鋼板を、圧下率
４０％以上８０％以下で冷間圧延を行うのは、通常の冷
延鋼板と同様で成品の寸法精度、形状性の向上の他再結
晶集合組織を改善するだめであり、８０係以上の圧下は
圧延全荷重が大きくなり作業性の低下、板厚精度平坦な
どの劣化をもたらし、又冷延鋼板として必要な板厚精度
、形状性を確保するだめには４０係以上の圧下率が必要
であり、又４０係以下では良好な絞り性が得られないか
らである。In addition, cold rolling a steel plate whose surface has been descaled by pickling at a reduction rate of 40% to 80% is the same as for ordinary cold rolled steel sheets, and improves the dimensional accuracy and shape of the finished product. In addition, it is impossible to improve the recrystallization texture, and rolling by a factor of 80 or more increases the total rolling load, resulting in a decrease in workability and deterioration of the plate thickness accuracy and flatness. This is because a rolling reduction ratio of 40 parts or more is required to ensure shapeability, and good drawability cannot be obtained with a reduction ratio of 40 parts or less.
実施例
次に、深絞り用冷延鋼板の製造過程を例にとってこの発
明法と従来法とを比較した実施結果を第１表に示し、か
つその成品の組成と焼なまし処理条件とを併せて示した
。Example Next, Table 1 shows the results of comparing the method of this invention and the conventional method, taking the manufacturing process of cold-rolled steel sheets for deep drawing as an example, and also shows the composition of the product and annealing treatment conditions. It was shown.
すなわち、上記第１表より、この発明の試料應１〜４３
は、従来法の試料４４ ｔＡ５に比べて、引張強さは大
差ないが、いずれも〒値を大幅に向上することができた
。That is, from Table 1 above, samples 1 to 43 of this invention
Compared to the conventional sample 44tA5, there was no significant difference in tensile strength, but both values were able to be significantly improved.
これにより、成形性がすぐれた深絞り用冷延鋼板が得ら
れることがわかる。It can be seen that this results in a cold-rolled steel sheet for deep drawing with excellent formability.
この発明は上記のごとく、連続炉なまし法において高温
度まで急熱せずに、予熱過程を有する再結高燐なまし処
理を施すことにより、アルミギルド鋼の深絞り用冷延鋼
板の製造に最も適した再結高燐なましとなり、成形性が
すぐれ、深絞り用の冷延鋼板を容易に製造できるもので
ある。As mentioned above, this invention can be applied to the production of cold-rolled steel sheets for deep drawing of aluminum guild steel by performing re-condensation high phosphorus annealing treatment with a preheating process without rapidly heating to high temperatures in the continuous furnace annealing method. It is the most suitable high-phosphorus annealing, has excellent formability, and can easily produce cold-rolled steel sheets for deep drawing.
第１図はこの発明の再結高燐なまし過程のヒートパター
ンを示す図表、第２図〜第３図はこの発明の他の再結高
燐なまし過程のヒートパターンの実施例を示す図表であ
る。
Ｐ ｒ ｅ ＲＡ・・・焼なまし予熱温度域、ＲＡ・・
・再結高燐なまし温度域、ＯＡ・・・過時効処理温度域
、１ａｔ２ａ、３ａ・・・この発明法の再結高燐なまし
過程におけるヒートパターンの曲線例、１ｂ、２ｂ。
３ｂ・・・従来法の再結高燐なまし過程におけるヒート
パターンの曲線例。Figure 1 is a diagram showing the heat pattern of the reconsolidation high phosphorus annealing process of this invention, and Figures 2 and 3 are diagrams showing examples of the heat pattern of another reconsolidation high phosphorus annealing process of this invention. It is. P r e RA...Annealing preheating temperature range, RA...
- Reconsolidation high phosphorus annealing temperature range, OA... Overaging treatment temperature range, 1at2a, 3a... Curve examples of heat patterns in the reconsolidation high phosphorus annealing process of this invention method, 1b, 2b. 3b...An example of a heat pattern curve in the reconsolidation high phosphorus annealing process of the conventional method.
Claims (1)
ガン０．１０〜０．４０％、シん０．０３％以下、アル
ミニウム０．０２〜０．１５係、窒素０．００２５〜０
．０２０％、残部は実質的に鉄及び不可避的不純物より
なる鋼を通常の熱間圧延を施して６００℃以下３００℃
以上の温度でコイルに巻取り、酸洗後圧工率４０係以上
８０％以下で冷間圧延を行った後、３５０℃以上再結晶
温度以下の温度域に１０〜６０秒予熱保持し、引続き再
結晶温度以上８００℃以下の温度域に短時間保持して再
結高炉なましを行い、次いで２５０〜４５０°Ｃの温度
域に降温、又は２００℃以下まで急冷し、再加熱後２５
０〜４５０℃の温度域で過時効処理を施すことを特徴と
する成形性のすぐれた深絞り用冷延鋼板の製造法。1 carbon 0.10% or less, silicon 0.20% or less, manganese 0.10-0.40%, silver 0.03% or less, aluminum 0.02-0.15%, nitrogen 0.0025-0
．． 020%, the remainder essentially consisting of iron and unavoidable impurities, is subjected to normal hot rolling to a temperature of 600°C or lower and 300°C.
After winding into a coil at the above temperature and cold rolling at a rolling ratio of 40 to 80% after pickling, preheat and hold for 10 to 60 seconds at a temperature range of 350°C or higher and below the recrystallization temperature. Recrystallization blast furnace annealing is carried out by holding for a short time in a temperature range above the recrystallization temperature and below 800 °C, then the temperature is lowered to a temperature range of 250 to 450 °C, or rapidly cooled to below 200 °C, and after reheating 25
A method for producing a cold-rolled steel sheet for deep drawing with excellent formability, which comprises performing an overaging treatment in a temperature range of 0 to 450°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP55094336A JPS593527B2 (en) | 1980-07-09 | 1980-07-09 | Manufacturing method of cold-rolled steel sheet for deep drawing with excellent formability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP55094336A JPS593527B2 (en) | 1980-07-09 | 1980-07-09 | Manufacturing method of cold-rolled steel sheet for deep drawing with excellent formability |
Related Child Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16299883A Division JPS5974235A (en) | 1983-09-05 | 1983-09-05 | Production of cold-rolled steel sheet for deep drawing having excellent formability |
| JP16299783A Division JPS5974234A (en) | 1983-09-05 | 1983-09-05 | Production of cold-rolled steel sheet for deep drawing having excellent formability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5719333A JPS5719333A (en) | 1982-02-01 |
| JPS593527B2 true JPS593527B2 (en) | 1984-01-24 |
Family
ID=14107432
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP55094336A Expired JPS593527B2 (en) | 1980-07-09 | 1980-07-09 | Manufacturing method of cold-rolled steel sheet for deep drawing with excellent formability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS593527B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4591395A (en) * | 1983-05-05 | 1986-05-27 | Armco Inc. | Method of heat treating low carbon steel strip |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5320446A (en) * | 1976-08-07 | 1978-02-24 | Hiroyuki Yamato | Snack noodle packaed in container |
-
1980
- 1980-07-09 JP JP55094336A patent/JPS593527B2/en not_active Expired
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5320446A (en) * | 1976-08-07 | 1978-02-24 | Hiroyuki Yamato | Snack noodle packaed in container |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5719333A (en) | 1982-02-01 |
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