JPS5956528A - Manufacture of high-tension cold-rolled steel plate with superior formability - Google Patents

Abstract

PURPOSE:To provide superior formability and high tension to a steel contg. specified amounts of C, Si, Mn, P, Al and N by a continuous annealing method by subjecting the steel to recrystallization annealing through a preheating stage without carrying out rapid heating to a prescribed high annealing temp. CONSTITUTION:The composition of a steel is composed of, by weight, <0.15% C, <0.2% Si, 0.4-3% Mn, <0.2% P, 0.02-0.15% Al, 0.0025-0.02% N and the balance Fe. The steel is hot rolled as usual, coiled at 300-600 deg.C, pickled, and cold rolled at 40-80% draft. The cold rolled plate is preheated at 350 deg.C- the recrystallization temp. for 10-60sec and held at the recrystallization temp. -850 deg.C for a short time to carry out recrystallization annealing. It is then overaged at 250-450 deg.C.

Description

【発明の詳細な説明】 この発明ζよ、成形性のすぐれた高張力冷延鋼板の製造
法に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention ζ relates to a method for producing high-strength cold-rolled steel sheets with excellent formability.

冷延鋼板の製造法は、周知のごとく、熱間仕ｌ−圧延機
で圧延（７た倒板をダウンコイヲで巻取った後、酸洗→
冷間圧延→表面清浄−焼なま１７・・・・・・・・・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鉋に変って、アｌレミキルド鋼が使
用されるよ・）になってきた。これは、高強度鋼素材で
あると共に成分偏析にもとづく特性変動が少なく、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Ｎを焼なま
し処理工程中に微細なＡＩＮ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ワンクツオード値（
以下７値と称す〕を高いレベルに持ちきたすことができ
るためである。As is well known, the manufacturing method for cold-rolled steel sheets is rolling with a hot rolling mill (after rolling the flattened sheet with a down-roller, pickling →
Cold-rolled steel sheets are manufactured through the following processing steps: cold rolling → surface cleaning → annealing Steel is now being used. Not only is this a high-strength steel material, there are few changes in properties due to component segregation, and it is resistant to aging, but the batch annealing method eliminates nitrogen N dissolved in the material. It is precipitated as fine AIN during the annealing process to improve formability (
Wanktsuode value (deep drawability) is used as an index of
This is because it is possible to bring the 7 values (hereinafter referred to as 7 values) to a high level.

ところが、連続焼なまし法においては、このアルミギル
ド鋼の特徴であるところの微細なＡＩＮの析出によるＴ
値の向上が一般的に難しい。これは昇熱速度が速いため
、微細ＡｌＮの析出後、再結晶が進行するという順序が
逆転又はこれに近い状態になることによる。これは、涼
続焼なまし法において、Ａ５Ｎ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。However, in the continuous annealing method, T due to the precipitation of fine AIN, which is a characteristic of this aluminum guild steel,
It is generally difficult to improve the value. This is because the heating rate is fast, so that the order in which recrystallization proceeds after precipitation of fine AlN is reversed or a state close to this occurs. In the continuous cool annealing method, this does not provide any precipitation effect as A5N, and also inhibits recrystallized grain growth.

そこで、連続焼なまし法における、このＴ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 for improving the T value in the continuous annealing method.

すなわち、 １、熱間圧延後の鋼板の巻取りを、高温巻取りとするこ
とにより、炭化物の凝集及びＡＩＨの大型析出物の析出
を施し、Ｔ値の向−にと再結晶粒成長を図ったもの。Namely, 1. By winding the steel sheet after hot rolling, high-temperature winding is performed to cause agglomeration of carbides and precipitation of large precipitates of AIH, and to aim for recrystallized grain growth in the direction of the T value. Something.

２、連続炉での再結品位なまし温１２を通常より昇温さ
せ、その鋼板の組織をフェライト十オーヌテナイト領域
まで昇温して集合組織の改善を図り、Ｔ値の向１を目脂
したもの。2. Re-solidification grade annealing temperature 12 in a continuous furnace was raised higher than usual to improve the texture of the steel sheet to the ferrite-10-o-nutenite region, and the T value was increased to 1. thing.

８、チタンを添加することによりＴ値の向上を図ったも
の等がある。8. There are some products in which the T value is improved by adding titanium.

しかし、上記】、の高温巻取りを行うと、脱スケール性
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１′、↓祠としては格落ちする場合が多くなる
。又、２．の再結品位なまし温度を上げると、連続炉に
要する灼料原単位が増大し、コストアップとなる。又、
８．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。However, when high-temperature winding of the above] is performed, descaling properties and surface properties deteriorate, coarsening of crystal grains, defective shapes, etc. occur, and the quality of cold-rolled 1' and ↓ shrines is often degraded. . Also, 2. Increasing the annealing temperature for reconsolidation increases the unit consumption of caustic material required for continuous furnaces, which increases costs. or,
8. When titanium is added, titanium combines with carbon, so when adding titanium, a vacuum decarburization treatment must also be performed at that time, which has the disadvantage of increasing costs due to that treatment and the use of titanium. .

この発明は、これらの方法をとらず、連続焼／、［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８５〜６０ｋｙ／
−クヲヌの高張力冷延鋼板の製造法を提案するものであ
る。The present invention does not use these methods, but by partially changing the heat pattern in the continuous firing/burning process, the above-mentioned drawbacks can be overcome by producing a molding process of 85 to 60 ky/y
- We propose a method for producing Kuwonu's high-strength cold-rolled steel sheets.

すなわち、この発明は ｌ、炭素０．１５％以下、けい素０．２０％以下、マン
ガン０．４０〜３．０係、りん０，２０％以Ｆ、アルミ
ニウム０．０２〜０．１５％、窒素０．００２５〜０．
０２％、残部実質的に鉄よりなる銅を、通常の熱間圧延
を施して６００°Ｃ以下３００°Ｃ以上でコイルに巻取
り、酸洗後圧工率４０％以上８０係以下で冷間圧延を行
った後、８５０°Ｃ以上再結晶温度以下好ましくは４５
０〜５５０°Ｃの温度域に１０〜６０秒予熱保持し、引
続き１１結晶温度以−１＝　８　Ｆ＋　０°Ｃ以下の温
度域に短時間保持して再結品位なましを行い、次いで２
５０〜４５０°Ｃの温度域に降温して過時効処理を施す
ことを特徴とする成形性のすぐれた高張力冷延鋼板の製
造法。That is, this invention contains l, carbon 0.15% or less, silicon 0.20% or less, manganese 0.40 to 3.0%, phosphorus 0.20% or more F, aluminum 0.02 to 0.15%, Nitrogen 0.0025-0.
02%, the remainder substantially iron, is subjected to normal hot rolling, wound into a coil at 600°C or lower and 300°C or higher, and after pickling, cold rolled at a rolling rate of 40% or higher and 80% or lower. After rolling, the temperature is higher than 850°C and lower than the recrystallization temperature, preferably 45°C.
Preheat and hold for 10 to 60 seconds in a temperature range of 0 to 550°C, then hold for a short time in a temperature range of 11 crystallization temperature or less - 1 = 8 F + 0°C or less to annealing the re-solidification quality, then 2
A method for producing a high-strength cold-rolled steel sheet with excellent formability, which comprises lowering the temperature to a temperature range of 50 to 450°C and performing an overaging treatment.

２、上記第１項の成分に加えて、さらにクロム０．５チ
以下、モリブデン０．８％以下のうちどちらか一方、又
は両方を含有することを特徴とする成形性のすぐれた高
張力冷延鋼板の製造法を要旨とする。2. In addition to the components in item 1 above, a high-strength cooling material with excellent formability, which further contains one or both of 0.5% or less chromium and 0.8% or less molybdenum. The gist is the manufacturing method of rolled steel plates.

まず、この発明について具体的に説明ずろと、第１図に
示すように、曲線ｌＩＮはこの発明法の四結晶位なまし
及び過時効処理３Ｑ稈におりるｌｌ−１パターンの曲線
を示し、曲！’ｉ！Ｉｂは従来法の再結品位なまし及び
過時効処理過程］こおりるヒートパターンの曲線を示す
もので、連続炉にぢいてコ、イルを連続的に焼ｊ工まし
炉の中を通過さすながら連続位なましを行うが、まず幻
゛ｔなま［７初期の段階でいったん８５０”Ｃ以上〜再
結晶温度以下の温度範囲の位なまし予熱温度域（Ｐｒｅ
ＲＡ）で１０〜６０秒程度項時間保持する。この幻ンな
まし予熱２１ｉ度域（Ｐｏｐ　ＲＡ　）を施すことによ
り、冷延べｔ板中の窒素をＡＩＮとして微細に析出する
ようにしたものである、すなわち、アルミギルド（７１
は冷延後の再結品位なまし初期段階におい’ｒＡｅＮを
微細に析出させやずく、これにより再結晶粒成長Ｑを改
善し２、高７値の得られることが知られている。そこで
、発明者は連続焼なまし法においで、Ａ４Ｎの析出１２
やすい温度域に短時間保持することにより、ＡｅＮを十
分析出させて集合組織を改善（−５７値を向−１−せ（
。First, to explain this invention in detail, as shown in FIG. 1, the curve lIN shows the ll-1 pattern curve that falls on the 3Q culm of the tetracrystalline annealing and overaging treatment of this invention method, song! 'i! Ib shows the curve of the heat pattern of the conventional method for re-solidification grade annealing and over-aging treatment. Continuous annealing is performed, but first the phantom natural [7] At the initial stage, the annealing preheating temperature range (Pre
RA) for about 10 to 60 seconds. By performing this preheating in the 21i degree range (Pop RA), the nitrogen in the cold rolled T-sheet is finely precipitated as AIN.
It is known that 'rAeN is finely precipitated in the initial stage of recrystallization grade annealing after cold rolling, which improves the recrystallized grain growth Q and provides a high value of 2 and 7. Therefore, the inventor developed a continuous annealing method to prevent precipitation of A4N.
By keeping it in a temperature range that is easy to maintain for a short time, AeN is released sufficiently and the texture is improved (towards -57 value (-1-)).
.

め、成形性の向上を図るものである。The aim 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。すなわち、Ａ１変態点近傍の再結品
位なまし温度域（ＲＡ）まで昇温しで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。次いで、２５
０〜４５０°Ｃの過時効処理温度域（ＯＡ　）まで降温
して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。Then, the subsequent temperature process is performed in the same manner as in a normal heat pattern. That is, the temperature is raised to the recrystallization annealing temperature range (RA) near the A1 transformation point and held for about 20 to 120 seconds, during which it is softened through the process of recrystallization and grain growth to improve moldability. It is something. Then 25
This is a method in which the temperature is lowered to an overaging treatment temperature range (OA) of 0 to 450°C and held for 2 to 4 minutes to reduce solid solution carbon, which causes aging.

上記焼なまし予熱温度域（Ｐｒｅ　ＲＡ　）を３５０°
Ｃ以上〜再結晶温度以下としたのは、８５０　”Ｃ未満
ではＡＩＮ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ＡｄＮの析
出後再結晶させ、集合４１１ａを改善する」という目的
を得ることが困難と／；Ｊ：るためである。The above annealing preheating temperature range (Pre RA ) is 350°
The reason for setting the temperature to be between 850"C and below the recrystallization temperature is because if it is less than 850"C, the amount of heat necessary for AIN precipitation cannot be obtained, and if it exceeds the recrystallization temperature, "fine AdN will not be re-precipitated after precipitation" which is the purpose of this invention. This is because it is difficult to achieve the objective of "crystallizing and improving the set 411a."

又、その時間は１０秒以上保持すれば、その間に十分Ａ
４Ｎを析出させることができる。このＡｌｘ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」二限となる。Also, if you hold it for more than 10 seconds, you can get enough A during that time.
4N can be precipitated. The longer the Alx precipitation time is, the more preferable it is, but since this leads to an increase in the length of the equipment, the practical limit is about 60 seconds.

に記再結）へｒ口ヴなま（７淘バエ゛威（ＲＡ）は、再
結晶温度以上８５０”（３以下でよいが、炉の燃料原ｌ
Ｉｉ、位を考慮してできるだけ低い方がよい。この点に
関ｊ２、プエフィトー相組織６１の局舎は後述ｌ−る７
値の向」二により６５０〜７　ｆｉ　Ｏ”Ｃの温度範囲
でよいう又その保持時間は長い方が」；いが、設イｑｕ
　＋−許容範囲内の２０〜１２０秒程度で十分再結品位
ｆ工まし＃Ｌ　１１効果が得られる。一方フエフイト＋
マル１ンリイトの複合組織を有するいわゆる二相組枠Ｑ
１の場合再結品位なまＬ７温度はプエフイト（ａ）→−
オースデナイト（γ）域で均熱保持１７、γ相への成分
元素４．１化を図るため、７５０〜８５　（＋　”０が
必要である。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秒程度でその効果が得られる。又
、過時効処理温度（ＯＡ）は、通常と同じ２５０〜４ｆ
ｉＯ”（！の時効処理に適した温度範囲でよく、その時
間も通常と同じの２〜４分の時効処理時間で十分である
。RA is above the recrystallization temperature and 850" (it can be below 3, but the reactor's fuel source l
It is better to keep it as low as possible, taking into account the Ii. Regarding this point, the headquarters of the Puephyto phase organization 61 will be described later.
Depending on the direction of the value, a temperature range of 650 to 7 fi O"C is sufficient, and the longer the holding time, the better.
+-A sufficient re-coalescence quality improvement #L 11 effect can be obtained in about 20 to 120 seconds within the allowable range. On the other hand, Huefuit+
The so-called two-phase framework Q with a composite structure of Maru-1-reit
In the case of 1, the re-solidification grade raw L7 temperature is Puefuit (a) → -
In order to hold the temperature uniformly in the ausdenite (γ) region at 17, and to convert the component elements to 4.1 into the γ phase, 750 to 85 (+ “0” is required. The longer the holding time is, the more the equipment allows. The effect can be obtained within the range of 20 to 120 seconds.Also, the overaging treatment temperature (OA) is 250 to 4f, which is the same as normal.
The temperature range suitable for aging treatment of iO'' (!) may be used, and the aging treatment time of 2 to 4 minutes, which is the same as usual, is sufficient.

上記暁なまシ、、炉内における焼なま【、の予熱（や作
は、炉内の温度調整を行うことにより、容易にこの発明
の１．：’ＩＱ　ｆ、ｃま１．゛ｒ−菖帯を設ｉＪるこ
とができる。By preheating the above-mentioned annealing in the furnace, by adjusting the temperature in the furnace, it is possible to easily obtain the - You can set up irises.

このようｌｒＬ、再結晶ｊｐ、’ｐ　ｆｌまし時のＩ−
一トパターンを一部？（にえるのろて、成品の７値が向
−１ニし、成形性がづ°ぐれ、ひす′口時効の発生を抑
制した高品質の成品５：　！ｌ”Ｊａ　′するξとがで
きる。このＶ値の同士に佇い、下記に示す種々の問題も
解消される。Like this lrL, recrystallization jp, 'p fl
Part of the pattern? (At the end of the day, the 7 value of the finished product is towards -1, the formability is distorted, and the occurrence of aging is suppressed. High quality product 5: !l"Ja' ξ .With these V values, various problems described below can be solved.

ずｌλわち、ダウンコイラでの７５０°Ｃ前後の高温巻
取りを要仕り゛、コイルの巻取温バ［を６００°Ｃ以下
にしても１［“１ｒ実に７値の向−１二を図ることがで
きる。したがって、高ｌ原巻Ｊｉりにより生じる脱スケ
ール性、表面性状の悪化″？）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。In other words, it is necessary to wind the coil at a high temperature of around 750°C in the down coiler. Therefore, the descaling property and surface quality deteriorated due to high original rolling. ) It is possible to suppress coarsening of crystal grains, poor shape, etc., and it is possible to obtain an optimal cold-rolled base material.

又、再結品位なま［７温度域（ＲＡ）は、通常集合組９
．大の改善を図って１値を向」―シ得るように、短時間
内に７００〜８５（１”Ｏ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Ｔ値を向ヒし得
るものであるから、フエフィトー相組織ζ１のり４合百
結品位なま１．温度域（ＲＡ）を６５０〜７５０“Ｃ程
度まで下げることができる。このため、連続炉における
１然料原ｒド４１’ｒを（ｉｊ”Ｉｌ実１こ低減て５ｓ
る。In addition, the reconsolidation quality raw [7 temperature range (RA) is normal set group 9
．． The temperature was raised to 700 to 85 (1"O) within a short period of time in order to achieve a T value of 1" with a great improvement. Therefore, the temperature range (RA) can be lowered to about 650-750"C. Reduce the raw material r de 41'r by 1 5s
Ru.

又、ｆ−クンの添加や真空脱１１，１遣処叩ｆ工ども’
、；ｊｊ　４ｊンＪ”、きわめＴ：　ｒ、１　、’ｔ（
かつ１ｊ（Ｉｔ実に７値の向１−を得ることができる。Also, the addition of f-kun and the vacuum removal 11.1.
, ;jj 4jnJ", extremelyT: r,1 ,'t(
And 1j(It can indeed obtain 7-valued direction 1-).

又、この発明のアルミベールド４悶冷４［、Ｘ７４板は
、例えば；ＩＩ！続鋳造法又は造塊法によりＩ！Ｉ＋Ｊ
造１．、　ｌｌ−凸張力冷延鋼板、二用組織高張力冷延
羽板などが対二Ωとなる。In addition, the aluminum veiled 4[,X74] plate of this invention can be used, for example; II! I! by continuous casting method or ingot forming method! I+J
Construction 1. , ll-convex tension cold-rolled steel sheets, two-structure high-tensile cold-rolled blades, etc. are 2Ω.

この発明番こおいで、鋼の化学成分をＩＸ１番定したの
は次の理由による。The reason why the chemical composition of steel was determined as IX1 in this invention is as follows.

炭素は、強ＩＩ［を得るために必要ｌｘ元素であるが、
炭素が０．１５％を越えると、溶接性がＷｊ化ｔろため
、０．１５％以下とした。Carbon is an lx element necessary to obtain strong II, but
If carbon exceeds 0.15%, weldability deteriorates, so the carbon content was set to 0.15% or less.

けい素は、０．２０％を越えると、５譲反表面番こ灯７
４　／工まし時に着色し、又スケールによる表面欠陥と
ｆλるため、０．２０チ以Ｆとした。If silicon exceeds 0.20%,
4/In order to avoid coloring during machining and surface defects caused by scale, the F value was set to 0.20 cm or more.

マンガンは、強度を得るために必要ｆ（元素であるが、
０．４０チ未満では目標とする強バ（を得るには十分で
なく、フエフイトー相ｒ１１の場合はマンＪｆン量は０
．４０〜１，５．０％が適しているが、一方フエフイト
トマルテン用イトニ相１の局舎のマンガン量はＩＪヂ・
以］−が必要であるが、８．０チを越えると溶製が困９
“１Ｆで′あり、かつコスｔＲとなルｔ、め、０．４（
１〜８．０グとしｌ、−６ りんＣ」、高張力化１こ必要であるが、０．２０チを越
えると、二次１１］１工脆化の危険性があり、又ヌボッ
ト溶接什が劣化するため、０．２０％以下とした。Manganese is an element required to obtain strength.
If it is less than 0.40, it is not enough to obtain the target strong power, and in the case of Huehuito phase r11, the amount of man Jf is 0.
．． 40 to 1.5.0% is suitable, but on the other hand, the amount of manganese in the phase 1 for Fehuitomarten is IJji.
] - is required, but if it exceeds 8.0 inches, it will be difficult to melt.
“There is ' on the 1st floor, and the cost tR is 0.4 (
1 to 8.0 g, -6 phosphorus C'', high tension is necessary, but if it exceeds 0.20 g, there is a risk of secondary embrittlement, and Nubot welding The content was set at 0.20% or less since the content deteriorates.

ｒルミニラＪ・は、　ＡｅＮの析出番こ必要で、０．０
２チ未満では効果が少なく、０．１５チを越えるとスラ
ブ加熱時のＡｊＮの同溶化が不完全となり、結晶粒の微
細化により延性が低下するため、０，０２〜（１，１５
チと１．た。r Luminilla J. requires the precipitation number of AeN, which is 0.0
If it is less than 2 inches, the effect will be small, and if it exceeds 0.15 inches, the isosolubilization of AjN will be incomplete during heating of the slab, and the ductility will decrease due to grain refinement.
Chi and 1. Ta.

Ｃ８素は、伸びを向ヒさせるためには少ない方がよいが
、（）、■）２５チ未満ではＡ／Ｎの析出が不十分であ
り、０．０２％９越えると伸びが低下し、アルミニウド
と相俟ってスラブ加熱時のＡ　ｇ、Ｎの固溶化が不完全
となるため、ｎ、００２５〜０．　（＋　２チとした。It is better to have less C8 element in order to improve elongation, but (), ■) If it is less than 25 inches, precipitation of A/N is insufficient, and if it exceeds 0.02%9, elongation decreases. Combined with aluminum, the solid solution of Ag and N during slab heating becomes incomplete, so n, 0025 to 0. (I set it as +2.

クロノ、は、強度向−１−のため及び二相組織化にあた
り、マンガ／ｒ１１の低減に有効であるが、０．５９’
、を越えると、添加のわりにこれらの効果のと昇が少な
い］；むしろ集合組織を劣化させるので、（ＩＪＯチ以
下とした。Chrono is effective in reducing Manga/r11 due to strength direction -1- and two-phase organization, but 0.59'
If it exceeds IJO, the increase in these effects will be small compared to the addition]; on the contrary, it will deteriorate the texture, so it was set to be below (IJO).

又、モリブデンも同様の理由により＋１．　Ｒｌ）チ以
トとした。Also, molybdenum is also +1 for the same reason. Rl)

熱間仕上圧延後の巻取温度を６００°Ｃ以Ｆｌ’１００
’Ｃ以上としたのは、６００℃を越えると、巻取後の冷
却中に大型のＡ／Ｎが析出【７てしまい、本来の目的で
あるところの予熱温度域（Ｐｒｅ　ＲＡ　）での微細な
ｈ（ＪＮの析出が不可能となるため、６００″Ｃ以下と
【７た。又、８００℃以下では巻取時の銅帯強度が強く
、巻取が困難となり、製造上の不具合を生じたり、水冷
却のための水Ｒを増大、または能率の低下をきたす。一
方で８００℃以下としても、絞り性向！・に対する効果
は変らない。Coiling temperature after hot finish rolling is 600°C or higher Fl'100
The reason for setting it above 600℃ is that if the temperature exceeds 600℃, large A/N particles will precipitate during cooling after winding. (Since precipitation of JN becomes impossible, the copper strip should be kept under 600"C [7. This may increase the amount of water R for water cooling, or reduce efficiency.On the other hand, even if the temperature is lower than 800°C, the effect on the drawing tendency will not change.

又、冷間圧下率を４０チ以」−８０％以下と１７だのは
、通常の冷延鋼板と同様で成品寸法精度、形状性の向上
の他、再結晶集合組織を改善するためであり、８０チ以
上の圧下は圧延全荷重が大きくなり作業性の低下、板厚
精度平担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、形状性を確保するためには４０チ以十、
の圧下率が必要で；【）す、圧下率４０チ以下では良好
な絞り性が得られないからである。In addition, the cold rolling reduction ratio of 40 inches or less - 80% or less is 17, which is the same as for ordinary cold rolled steel sheets, in order to improve the recrystallization texture as well as improve the product dimensional accuracy and shape. A reduction of 80 inches or more increases the total rolling load, resulting in decreased workability and poor plate thickness accuracy.In addition, in order to ensure the thickness accuracy and shape required for cold-rolled steel sheets, 40 inches or more is required. Chii ten,
A rolling reduction ratio of 40 inches or less is necessary; this is because good drawing properties cannot be obtained with a rolling reduction ratio of 40 inches or less.

〔実施例１］ 次に、高張力冷延口板試料Ａ　Ｉ、　２．８．８と、二
相組織高張力冷延ｑ板試料Ａ　４．５．６．７．９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、その成品の組成と位ｊ工ま１２
処理条件もイ）１せて示した。[Example 1] Next, the manufacturing process of high-tensile cold-rolled plate sample A I, 2.8.8 and two-phase structure high-tensile cold-rolled q-plate sample A 4.5.6.7.9 will be described as an example. Table 1 shows the results of a comparison between this invention method and the conventional method, and shows the composition of the product and the process.
The processing conditions are also shown in 1).

（以下余白） 上記第１表よりわかるごとく、この発明法によるもの試
料Ａｌ〜７は従来法によるもの試料ＡＱ。(The following is a blank space) As can be seen from Table 1 above, samples Al to 7 produced by the method of this invention are samples AQ produced by the conventional method.

９に比べていずれもｊ値が大幅に向Ｉ・ずろことが認め
られる。これは、仁の発明法のＡｇＮを析出させるとい
う予熱條なまし操作が７値の向ｌ−に音（７く貢献した
ものである。It can be seen that the j values are significantly more positive and negative compared to 9. This is because the preheating condition annealing operation of precipitating AgN in Jin's invention contributed to the 7-value direction.

この発明は上記のごとく、連続焼なまし法において所定
の焼なまし高温１店まで急熱せずに、予熱過程を経て、
再結品位なまし処理を施すこと番こより、アルミギルド
鋼の高張力冷延≦１板の製造に最も適した再結品位なま
し法で直弾１）［を有し、か゛つ、成形性にすぐれた高
張力冷延倒板を低コア、１で、しかも容易に製造できる
ものである。As mentioned above, in the continuous annealing method, this invention does not rapidly heat up to a predetermined annealing high temperature, but instead undergoes a preheating process.
The resetting grade annealing process is the most suitable method for manufacturing high tensile strength cold rolled aluminum guild steel sheets. To provide a high-tensile cold-rolled board with excellent properties and a low core, and to easily produce it.

【図面の簡単な説明】[Brief explanation of drawings]

ｖｇ１図はこの発明の再結品位なまし過程のヒートパタ
ーンを示す図表である。 ｐｒｅ　ＲＡ・・・位なまし予熱温度域、ＲＡ・・・再
結品位なまし温度域、ＯＡ・・・過時効処理温度域、ｌ
ａ・・・この発明法の再結品位なまＩ７過程匿おけるヒ
ートパターンの曲線例、Ｉｂ・・・従来法の再結品位な
まＬ　ｊＭ＋程番こおけるヒートパターンの曲線例。 出願人　　住友金属工業株式会社Figure vg1 is a chart showing the heat pattern of the re-solidification quality annealing process of this invention. pre RA...Annealing preheating temperature range, RA...Reconsolidation grade annealing temperature range, OA...Overaging treatment temperature range, l
a... An example of a curve of a heat pattern obtained by the method of the present invention with a reconsolidation quality of I7, and Ib... An example of a curve of a heat pattern obtained by a conventional method with a reconsolidation quality of I7. Applicant: Sumitomo Metal Industries, Ltd.

Claims (1)

【特許請求の範囲】 １　炭素０．１５　％以下、けい素０．２０％以ド、マ
ンガン０．４０〜８．０係、りん０，２０％以下、アル
ミ、＝ウム０．０２〜０．１５チ、窒素０．００２５〜
０．０２％、残部実質的に鉄よりなる泪を、通常の熱間
圧延を施【、て６００　”Ｃ以下８００”Ｃ以−にでコ
イルに巻取り、酸洗後圧工率４０チ以上８０チ以丁で冷
間圧延を行った後、８６０°Ｃ以」−再結品温ＩＷ以Ｆ
の温度域に１０〜６０秒予熱保持し、引続き再結晶温度
以上８５０°Ｃ以下の温度域に短時間保持して再結黒焼
なましを行い、引続いて２５０〜４５０°Ｃ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高
張力冷延鋼板の製；Ｈ＋Ｈ法。 ２　炭素０．１６％以下、けい素０．２０％以下、マン
ガン０．４０〜ａ、ｏｑＡｌりん０．２０チ以Ｆ、アル
ミニウム０．０２〜０．１５チ、窒素０．００２５〜０
．０２％にさらにクロＪ、＋１．ｉ以下とでリプダン０
．８係以下のうちの１種又は２種を含有さ時、残部実質
的に鉄よりなる鋪を、通常の熱間田延を施しで６００′
”Ｃ以ド８００°Ｃ以上でコイルに巻取り、贋洗後圧下
率４０チ以１−８０係以下で冷間圧延を行った後、８ｆ
ｉＯ℃以−１．再結晶温度以下の温度域に１０〜６０秒
′に一熱保持１２、引続き再結晶温度以ト８５０”０以
下の温度域に短２５０〜４５０”Ｃ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高張力冷延
鋼板の製造法。[Claims] 1 Carbon: 0.15% or less, silicon: 0.20% or more, manganese: 0.40 to 8.0%, phosphorus: 0.20% or less, aluminum, =umium: 0.02 to 0.0%. 15chi, nitrogen 0.0025~
0.02%, the remainder being substantially iron, was subjected to conventional hot rolling and wound into a coil at a temperature of 600"C or less or 800"C or more, and after pickling, the rolling rate was 40mm or more. After cold rolling with 80 inch rolls, the temperature of the re-solidified product is 860°C or higher, IW or higher.
Preheat and hold for 10 to 60 seconds in a temperature range of Production of high-strength cold-rolled steel sheets with excellent formability characterized by subjecting them to over-aging treatment; H+H method. 2 Carbon 0.16% or less, silicon 0.20% or less, manganese 0.40 to a, oqAl phosphorus 0.20 or more F, aluminum 0.02 to 0.15, nitrogen 0.0025 to 0
．． 02% plus Kuro J, +1. Reputation 0 with below i
．． When it contains one or two of the following elements, the remaining part is essentially made of iron and is rolled for 600 minutes by ordinary hot rolling.
Winding into a coil at a temperature of 800°C or higher, after washing, cold rolling at a rolling reduction of 40cm to 1-80cm, then 8f
iO℃ or below -1. Hold heat for 10 to 60 seconds in a temperature range below the recrystallization temperature, and then perform an overaging treatment in a short temperature range of 250 to 450"C in a temperature range below the recrystallization temperature and 850"0. A manufacturing method for high-strength cold-rolled steel sheets with excellent formability.