JP2705461B2 - Method of manufacturing cold rolled steel strip with excellent workability - Google Patents
Method of manufacturing cold rolled steel strip with excellent workabilityInfo
- Publication number
- JP2705461B2 JP2705461B2 JP14814792A JP14814792A JP2705461B2 JP 2705461 B2 JP2705461 B2 JP 2705461B2 JP 14814792 A JP14814792 A JP 14814792A JP 14814792 A JP14814792 A JP 14814792A JP 2705461 B2 JP2705461 B2 JP 2705461B2
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- Japan
- Prior art keywords
- annealing
- rolled steel
- steel
- cold
- steel strip
- 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 - Fee Related
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Description
【０００１】[0001]
【産業上の利用分野】この発明は、強度ならびに延性が
要求されるプロジェクション溶接用細粒鋼、薄物冷延鋼
板等として適した加工性に優れた冷延鋼帯の製造方法に
関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a cold-rolled steel strip excellent in workability and suitable as a fine-grained steel for projection welding, a thin cold-rolled steel sheet, or the like, which requires strength and ductility.
【０００２】[0002]
【従来の技術】プロジェクション溶接は、母材の片側ま
たは両側に小さな突起（ｐｒｏｊｅｃｔｉｏｎ）を作っ
てこの部分に大電流と加圧力を集中させ、母材の接触抵
抗と固有抵抗による抵抗発熱を利用し、溶接部を溶融せ
しめ、圧接を行うものである。プロジェクション溶接に
おいては、突起の形状寸法（高さ、先端太さ）によって
溶接部の品質が大きく左右されるので、突起の形状寸法
は通電前の予圧に十分耐えられるだけの剛性があり、か
つ相手の平板との熱平衡を保ちうることが必要である。
このため、ベアリングリテーナー等のプロジェクション
溶接用材料には、十分な突起高さを得るための延性と、
通電前の予圧に十分耐えられるだけの強度が必要であ
る。2. Description of the Related Art In projection welding, a small projection is formed on one or both sides of a base material to concentrate a large current and a pressing force on this portion, and the resistance heat generated by the contact resistance and the specific resistance of the base material is used. In this case, the welded portion is melted and pressed. In projection welding, the quality of the weld is greatly affected by the shape and size (height and tip thickness) of the projection. Therefore, the shape and size of the projection are sufficiently rigid to withstand the preload before energization, and It is necessary to be able to maintain the thermal equilibrium with the flat plate.
For this reason, projection welding materials such as bearing retainers have ductility to obtain a sufficient projection height,
It is necessary to have enough strength to withstand the preload before energization.
【０００３】上記強度ならびに延性が要求される加工性
に優れたベアリングリテーナー用材料、スチールペーパ
ー用材料、深絞り用材料等には、成分、フェライト結晶
粒度および展伸度等を調整した細粒鋼の冷延鋼板が使用
されている。一般的な箱形焼鈍炉による細粒鋼の製造方
法としては、冷間圧延したのち、箱形焼鈍炉でオープン
コイル焼鈍し、コイルの加熱速度を上昇させて急速加熱
を行う方法、熱間圧延時のコイル巻取り温度を６８０℃
以上の高温とし、高温巻取りを行う方法が知られてい
る。また、連続焼鈍炉による細粒鋼の製造においては、
図４に示すとおり、焼鈍加熱速度が極めて大きくなる
と、鋼中のｓｏｌ．Ａｌ量にかかわらず、等軸細粒組織
が得られる。これはＡｌＮの析出より早期にフェライト
粒の再結晶が起こるためである。[0003] Materials for bearing retainers, steel paper, and materials for deep drawing, which are excellent in workability requiring the above-mentioned strength and ductility, include fine-grained steel whose components, ferrite grain size and elongation are adjusted. Cold-rolled steel sheet is used. As a method for producing fine-grained steel using a general box-shaped annealing furnace, cold rolling is performed, then open coil annealing is performed in a box-shaped annealing furnace, and the heating rate of the coil is increased to perform rapid heating. Coil winding temperature at 680 ℃
A method of performing the high-temperature winding at a high temperature as described above is known. In the production of fine-grained steel by a continuous annealing furnace,
As shown in FIG. 4, when the annealing heating rate becomes extremely high, the sol. Regardless of the amount of Al, an equiaxed fine grain structure can be obtained. This is because recrystallization of ferrite grains occurs earlier than the precipitation of AlN.
【０００４】また、他の方法としては、Ｃ：０．０１〜
０．１０％、Ｍｎ：０．４０％、ｓｏｌ．Ａｌ：０．０
８０〜０．８５０％、Ｎ：０．００５０％以下を含有
し、残部は実質的にＦｅよりなるアルミキルド鋼を通常
の熱間圧延および冷間圧延後６７０〜７２０℃の通常の
焼なましを施しフェライト粒度を９以上の細粒にし、ｒ
値を１．５０以上とする鋼板（特開昭５４−８０２２５
号公報）、Ｃ：０．０２〜０．１２％、Ｍｎ：０．１〜
０．６％、Ｐ：０．０１〜０．０５％、Ａｌ：０．０８
％以下、残Ｆｅおよびその他不純物からなる低炭素鋼板
を連続焼鈍ラインにて再結晶温度以上Ａｃ１変態点以下
に加熱、均熱後、冷却速度を３〜１０００℃／ｓに調整
する熱処理を施し、硬度の異なる鋼板を作り分ける方法
（特開昭５７−７０２２７号公報）、Ｃ：０．０１０〜
０．０４０％、Ｍｎ：０．０５〜０．２５％、Ｓ：０．
００４〜０．０２０％、Ａｌ：０．０１０〜０．０８０
％、Ｎ：０．００３０％以下を含有し、残部がＦｅおよ
び不可避的不純物よりなる鋼を連続鋳造し、その直後の
鋳片（スラブ）を５０℃／ｍｉｎ以下の冷却速度で１１
００〜１２００℃まで冷却したのち、スラブ表面温度が
１０００〜１１００℃の温度域にあるときに熱延を開始
し、６５０℃以上の温度域で巻き取ったのち、冷延およ
び連続焼鈍を行う方法（特開平１−２０８４１９号公
報）等が提案されている。[0004] As another method, C: 0.01 to
0.10%, Mn: 0.40%, sol. Al: 0.0
Aluminum-killed steel containing 80 to 0.850%, N: 0.0050% or less, and the balance substantially consisting of Fe is subjected to ordinary annealing at 670 to 720 ° C after ordinary hot rolling and cold rolling. Ferrite grain size of 9 or more, r
Steel sheet having a value of 1.50 or more (Japanese Patent Laid-Open No. 54-80225).
Publication), C: 0.02-0.12%, Mn: 0.1-
0.6%, P: 0.01 to 0.05%, Al: 0.08
% Or less, a low carbon steel sheet comprising residual Fe and other impurities is heated to a recrystallization temperature or higher and an Ac1 transformation point or lower in a continuous annealing line, and after soaking, heat treatment for adjusting a cooling rate to 3 to 1000 ° C./s is performed. A method of separately producing steel sheets having different hardnesses (Japanese Patent Application Laid-Open No. 57-70227), C: 0.010
0.040%, Mn: 0.05-0.25%, S: 0.
004 to 0.020%, Al: 0.010 to 0.080
%, N: 0.0030% or less, with the balance being Fe and unavoidable impurities, continuously cast steel, and the slab immediately after that is cooled at a cooling rate of 50 ° C./min or less to 11%.
After cooling to 00 to 1200 ° C, a method in which hot rolling is started when the slab surface temperature is in a temperature range of 1000 to 1100 ° C, and is wound in a temperature range of 650 ° C or higher, and then cold rolling and continuous annealing are performed. (JP-A-1-208419) and the like have been proposed.
【０００５】[0005]
【発明が解決しようとする課題】前記プロジェクション
溶接性等の優れた等軸細粒鋼を製造するためには、前記
図４に示すとおり、ｓｏｌ．Ａｌ量を低下させ、焼鈍加
熱速度を上昇させてＡｌＮの析出に先立って再結晶さ
せ、なおかつ低い焼鈍温度で焼鈍し、フェライト結晶粒
の細粒化を図る必要がある。しかしながら、前記連続焼
鈍による細粒鋼の製造においては、焼鈍加熱速度が大き
く、等軸細粒鋼となるが、設備制約上焼鈍時間が制限さ
れ、最大２分程度であるため、焼鈍温度を７５０〜９０
０℃と高温にせざるを得ず、フェライト結晶粒が成長
し、フェライト結晶粒度番号は、最大でも１０のレベル
である。したがって、等軸細粒組織が得られる加熱速度
で、かつ、焼鈍温度を低くすることが必要である。In order to produce the equiaxed fine-grained steel having excellent projection weldability and the like, as shown in FIG. It is necessary to reduce the amount of Al, increase the annealing heating rate, recrystallize prior to the precipitation of AlN, and furthermore, anneal at a low annealing temperature to reduce the size of ferrite grains. However, in the production of fine-grained steel by the continuous annealing, the annealing heating rate is high and the steel is equiaxed fine-grained steel. However, the annealing time is limited due to facility restrictions, and the maximum annealing time is about 2 minutes. ~ 90
The temperature must be as high as 0 ° C., ferrite crystal grains grow, and the ferrite crystal grain size number is at most a level of 10. Therefore, it is necessary to reduce the annealing temperature at a heating rate at which an equiaxed fine grain structure is obtained.
【０００６】また、箱形焼鈍炉による細粒鋼の製造にお
いては、タイト焼鈍の場合に、窒素５０％以上、残部水
素からなる通常の焼鈍雰囲気では、焼鈍加熱速度は１５
℃／Ｈｒ程度と低く、等軸細粒鋼を得ることができな
い。箱形焼鈍炉でもオープンコイル焼鈍、または水素濃
度９０％以上、残部窒素の焼鈍雰囲気で焼鈍すれば、焼
鈍加熱速度を３０℃／Ｈｒ以上となるが、しかしこれだ
けでは等軸細粒鋼を得ることができない。[0006] In the production of fine-grained steel by a box-type annealing furnace, in the case of tight annealing, the annealing heating rate is 15 in an ordinary annealing atmosphere consisting of 50% or more of nitrogen and the balance of hydrogen.
[Deg.] C / Hr, so that equiaxed fine-grained steel cannot be obtained. Even in a box type annealing furnace, if the annealing is performed in an open coil annealing or an annealing atmosphere of hydrogen concentration 90% or more and the remaining nitrogen, the annealing heating rate becomes 30 ° C./Hr or more, but it is possible to obtain equiaxed fine-grained steel by itself. Can not.
【０００７】この発明の目的は、強度ならびに延性に優
れたフェライト結晶粒度番号１０以上の等軸微細粒鋼
を、箱形焼鈍炉により得ることことができる加工性に優
れた冷延鋼帯の製造方法を提供することにある。An object of the present invention is to produce a cold-rolled steel strip excellent in workability by which an equiaxed fine-grained steel having a ferrite crystal grain size number of 10 or more excellent in strength and ductility can be obtained by a box annealing furnace. It is to provide a method.
【０００８】[0008]
【課題を解決するための手段】本発明者らは、上記目的
を達成すべく鋭意試験研究を重ねた。その結果、熱延鋼
帯のｓｏｌ．Ａｌ量を０．０２５％以下とすれば、箱形
焼鈍炉で焼鈍加熱速度３０℃／Ｈｒで十分等軸細粒鋼が
得られること、また、焼鈍温度を７００℃以下とするこ
とによって、フェライト結晶粒度番号１０以上の微細粒
鋼を得ることができること、さらに、ｓｏｌ．Ａｌ量を
０．０２５％以下とすることにより、冷間圧延によって
導入された歪（ミクロ的には転位）が焼鈍によって加え
られる熱エネルギーにより開放（ミクロ的には転位の移
動）され易くなり、低い焼鈍温度でも再結晶し易くなる
ことを究明し、この発明に到達した。Means for Solving the Problems The present inventors have intensively studied and studied to achieve the above object. As a result, the sol. When the Al content is 0.025% or less, sufficient equiaxed fine-grained steel can be obtained with a box-type annealing furnace at an annealing heating rate of 30 ° C./Hr. It is possible to obtain a fine-grained steel having a crystal grain size number of 10 or more. By setting the Al content to 0.025% or less, the strain (dislocations in microscopy) introduced by cold rolling is easily released (dislocations in microscopy) by thermal energy applied by annealing, The present inventors have found that recrystallization is easy even at a low annealing temperature, and have reached the present invention.
【０００９】すなわちこの発明は、Ｃ：０．０２〜０．
１０％、Ｓｉ：０．０５％以下、Ｐ：０．０５０％以
下、Ｓ：０．０３０％以下、Ｍｎ：０．１０〜０．４０
％、ｓｏｌ．Ａｌ：０．００５〜０．０２５％を含有
し、残部がＦｅおよび不可避的不純物からなる熱延鋼帯
を、酸洗、冷間圧延したのち、水素濃度７５％以上の還
元性雰囲気ガス中で、加熱速度３０℃／Ｈｒ以上、焼鈍
温度５８０〜７００℃で箱焼鈍するのである。That is, according to the present invention, C: 0.02-0.
10%, Si: 0.05% or less, P: 0.050% or less, S: 0.030% or less, Mn: 0.10 to 0.40
%, Sol. Al: A hot-rolled steel strip containing 0.005 to 0.025%, with the balance being Fe and unavoidable impurities, is pickled and cold-rolled, and then reduced in a reducing atmosphere gas having a hydrogen concentration of 75% or more. The box annealing is performed at a heating rate of 30 ° C./Hr or more and an annealing temperature of 580 to 700 ° C.
【００１０】[0010]
【作用】この発明において、化学成分、還元性雰囲気ガ
ス中の水素濃度、箱焼鈍における加熱速度、焼鈍温度を
限定した理由は次のとおりである。Ｃは０．０２％未満
とするには精錬コストが上昇するので好ましくなく、
０．１０％を超えると鋼の硬化を増進させ、延性が劣化
するので加工用途には適さなくなるので、０．０２〜
０．１０％とした。Ｓｉは０．０５％を超えると強度が
上昇し、伸びが減少して加工用途には適さなくなるので
０．０５％以下とした。Ｐは０．０５％を超えるとＳｉ
と同様強度が上昇し、伸びが減少して加工用途には適さ
なくなるので０．０５％以下とした。Ｓは０．０３％を
超えると熱間加工性が低下し、表面疵が発生すると共
に、ＭｎＳ系介在物が増加し、冷汗加工性が低下するの
で、０．０３％以下とした。Ｍｎは０．１０％未満では
スラブ加熱中にＦｅＳによる赤熱脆性が発生するため
０．１０％以上必要であるが、０．４０％を超えるとＣ
と同様鋼の硬化を増進させ、延性が劣化するので加工用
途には適さなくなるので、０．１０〜０．４０％とし
た。ｓｏｌ．Ａｌは０．００５％未満では脱酸不足とな
ってＣＯガスによる連続鋳造スラブ表面にピンホール疵
が発生し、０．０２５％を超えると、焼鈍加熱段階での
ＡｌＮの析出に先立つ再結晶が十分でなくなるので、
０．００５〜０．０２５％とした。特に、ｓｏｌ．Ａ
ｌ：０．０２０％以下では、図２および図３に示すとお
り、再結晶温度が低下して５８０℃で再結晶が開始さ
れ、フェライト結晶粒度番号１１以上の極細粒鋼を得る
ことができ、板厚０．２ｍｍの極薄鋼板をタイト焼鈍し
ても、焼付きが発生することはない。In the present invention, the reasons for limiting the chemical components, the hydrogen concentration in the reducing atmosphere gas, the heating rate in box annealing, and the annealing temperature are as follows. If C is less than 0.02%, the refining cost increases, which is not preferable.
If it exceeds 0.10%, the hardening of the steel is promoted, and the ductility is deteriorated.
0.10%. If the content of Si exceeds 0.05%, the strength increases, the elongation decreases, and it is not suitable for processing applications. If P exceeds 0.05%, Si
In the same manner as described above, the strength is increased, the elongation is reduced, and it is not suitable for processing applications. If S exceeds 0.03%, hot workability is reduced, surface flaws are generated, MnS-based inclusions are increased, and cold sweat workability is reduced, so S is set to 0.03% or less. If Mn is less than 0.10%, red hot embrittlement due to FeS occurs during slab heating, so Mn must be 0.10% or more.
In the same manner as described above, the hardness of the steel is increased, and the ductility is deteriorated. sol. If the Al content is less than 0.005%, deoxidation becomes insufficient and pinhole flaws are generated on the surface of the continuously cast slab by the CO gas. If the Al content exceeds 0.025%, recrystallization prior to the precipitation of AlN in the annealing heating stage occurs. Will not be enough
0.005 to 0.025%. In particular, sol. A
At l: 0.020% or less, as shown in FIGS. 2 and 3, the recrystallization temperature is lowered, recrystallization is started at 580 ° C., and an ultrafine-grained steel having a ferrite grain size of 11 or more can be obtained. Seizure does not occur even when tight annealing a very thin steel plate having a thickness of 0.2 mm.
【００１１】箱形焼鈍炉における雰囲気ガス中の水素濃
度を７５％以上としたのは、水素濃度が７５％未満では
焼鈍加熱速度３０℃／Ｈｒ以上を得ることができず、等
軸細粒鋼を得ることができないからである。焼鈍加熱速
度を３０℃／Ｈｒ以上としたのは、ｓｏｌ．Ａｌ：０．
００５〜０．０２５％において、焼鈍加熱段階でＡｌＮ
析出に先立って再結晶させ、等軸細粒鋼を得るには、３
０℃／Ｈｒ以上が必要であるからである。焼鈍温度を５
８０〜７００℃としたのは、５８０℃は再結晶開始温度
であり、７００℃を超えるとフェライト粒が成長して粗
大化し、フェライト粒度番号１０以上の等軸細粒鋼を得
ることができないからである。The reason why the hydrogen concentration in the atmosphere gas in the box type annealing furnace is set to 75% or more is that an annealing heating rate of 30 ° C./Hr or more cannot be obtained if the hydrogen concentration is less than 75%, Because you cannot get The reason why the annealing heating rate was set to 30 ° C./Hr or more was that sol. Al: 0.
005-0.025%, AlN
To obtain equiaxed fine-grained steel by recrystallization prior to precipitation, 3
This is because 0 ° C./Hr or more is required. Annealing temperature 5
The reason why the temperature is set to 80 to 700 ° C. is that 580 ° C. is a recrystallization start temperature, and if it exceeds 700 ° C., ferrite grains grow and become coarse, and it is not possible to obtain an equiaxed fine-grained steel having a ferrite grain number of 10 or more. It is.
【００１２】この発明においては、ｓｏｌ．Ａｌ：０．
００５〜０．０２５％の熱延鋼帯を、酸洗、冷間圧延し
たのち、水素濃度７５％以上の還元性雰囲気ガス中で、
加熱速度３０℃／Ｈｒ以上、焼鈍温度５８０〜７００℃
で箱焼鈍するすることによって、焼鈍加熱段階でＡｌＮ
の析出に先立ってフェライト粒が再結晶し、しかもフェ
ライト粒の粒成長が抑制されて等軸細粒組織となり、フ
ェライト結晶粒度番号１０以上の等軸微細粒鋼を得るこ
とができ、加工性に優れた冷延鋼帯を製造することがで
きる。In the present invention, sol. Al: 0.
After hot-rolled steel strip of 005 to 0.025% is pickled and cold-rolled, in a reducing atmosphere gas having a hydrogen concentration of 75% or more,
Heating rate 30 ° C / Hr or more, annealing temperature 580-700 ° C
By performing box annealing with AlN at the annealing heating stage,
Prior to the precipitation of ferrite, the ferrite grains are recrystallized, and the grain growth of the ferrite grains is suppressed to form an equiaxed fine grain structure, so that an equiaxed fine grain steel having a ferrite grain size number of 10 or more can be obtained. Excellent cold rolled steel strip can be manufactured.
【００１３】[0013]
実施例１ 表１に示す化学成分の熱間圧延鋼帯を、酸洗、冷間圧延
したのち、表２に示すとおり、箱型焼鈍炉を用いて表２
に示すとおり、焼鈍加熱速度１６〜４０℃／Ｈｒ、焼鈍
温度５８５〜６９０℃、焼鈍均熱時間８〜１０時間で焼
鈍した。得られた各鋼帯より試料を採取し、ＪＩＳ Ｇ
０５５２に規定のフェライト結晶粒度試験方法に準じ
てフェライト結晶粒の展伸度および切断法により粒度番
号を測定した。その結果を表２に併記する。なお、従来
例３のみは、連続焼鈍を実施した。Example 1 A hot-rolled steel strip having the chemical composition shown in Table 1 was pickled and cold-rolled, and then, as shown in Table 2, was subjected to Table 2 using a box-type annealing furnace.
As shown in Table 2, annealing was performed at an annealing heating rate of 16 to 40 ° C / Hr, an annealing temperature of 585 to 690 ° C, and an annealing soaking time of 8 to 10 hours. A sample was collected from each of the obtained steel strips and subjected to JIS G
In accordance with the ferrite crystal grain size test method specified in No. 0552, the grain size number was measured by elongation and cutting method of the ferrite crystal grains. The results are also shown in Table 2. In addition, only the conventional example 3 performed continuous annealing.
【００１４】[0014]
【表１】 [Table 1]
【００１５】[0015]
【表２】 [Table 2]
【００１６】表１および表２に示すとおり、ｓｏｌ．Ａ
ｌ：０．０２５％以下、焼鈍加熱速度３０℃／Ｈｒ以
上、焼鈍温度５８０〜７００℃で箱焼鈍した本発明例１
〜４は、いずれもフェライト結晶粒の展伸度０．９８〜
１．０３、粒度番号１０．８〜１２．０と等軸微細粒鋼
である。これに対し比較例１〜３は、いずれもフェライ
ト結晶粒の展伸度０．９９〜２．３０、粒度番号７．６
〜８．５で、フェライト結晶粒の細粒化が不十分であ
る。As shown in Tables 1 and 2, sol. A
l: 0.025% or less, Example 1 of the present invention in which box annealing was performed at an annealing heating rate of 30 ° C / Hr or more and an annealing temperature of 580 to 700 ° C.
-4 are 0.98 or more of the elongation of ferrite grains.
It is an equiaxed fine-grained steel with a grain size number of 1.03 to 12.0. On the other hand, Comparative Examples 1 to 3 all had a ferrite crystal grain elongation of 0.99 to 2.30 and a particle size number of 7.6.
-8.5, the grain refinement of ferrite crystal grains is insufficient.
【００１７】実施例２ 表３に示すとおり、ｓｏｌ．Ａｌ量以外は同一の成分組
成の熱間圧延鋼帯を酸洗したのち、圧下率７５％で冷間
圧延して板厚０．５ｍｍの冷間圧延鋼帯となし、表４に
示す焼鈍条件で焼鈍した。得られた各鋼帯より試料を採
取し、機械的性質の試験を行った。その結果を引張強さ
と伸びとのバランスで図１に示す。Example 2 As shown in Table 3, sol. After pickling a hot-rolled steel strip having the same composition except for the amount of Al, cold-rolling was performed at a rolling reduction of 75% to form a cold-rolled steel strip having a thickness of 0.5 mm. Annealing conditions shown in Table 4 Annealed. A sample was taken from each of the obtained steel strips and tested for mechanical properties. FIG. 1 shows the results in terms of the balance between tensile strength and elongation.
【００１８】[0018]
【表３】 [Table 3]
【００１９】[0019]
【表４】 [Table 4]
【００２０】図１に示すとおり、本発明例５の場合は、
従来例４ないし６に比較し、高強度、高延性の加工性に
優れた冷延鋼板を製造することができる。As shown in FIG. 1, in the case of Example 5 of the present invention,
Compared with Conventional Examples 4 to 6, a cold-rolled steel sheet having high strength and high ductility and excellent workability can be manufactured.
【００２１】[0021]
【発明の効果】以上述べたとおり、この発明方法によれ
ば、フェライト結晶粒度番号１０以上の等軸微細粒鋼を
得ることができ、ベアリングリテーナー用材料あるいは
焼鈍時に焼付きし易い薄物焼鈍冷延鋼板等、強度ならび
に延性双方を要求される加工性に優れた冷延鋼帯を容易
に製造することができる。As described above, according to the method of the present invention, it is possible to obtain an equiaxed fine grain steel having a ferrite grain size number of 10 or more, which is a material for a bearing retainer or a thin annealed cold rolled sheet which is easily seized during annealing. It is possible to easily produce a cold rolled steel strip such as a steel sheet which is excellent in workability requiring both strength and ductility.
【図１】実施例２における引張強さと伸びとのバランス
を示すグラフである。FIG. 1 is a graph showing the balance between tensile strength and elongation in Example 2.
【図２】加熱速度５０℃／Ｈｒにおける冷延鋼板中のｓ
ｏｌ．Ａｌ含有量と焼鈍温度と硬度（Ｈｖ）との関係を
示すグラフである。FIG. 2 shows s in a cold-rolled steel sheet at a heating rate of 50 ° C./Hr.
ol. It is a graph which shows the relationship between Al content, annealing temperature, and hardness (Hv).
【図３】ｓｏｌ．Ａｌ含有量と加熱速度５０℃／Ｈｒに
おける焼鈍温度とフェライト結晶粒度番号との関係を示
すグラフである。FIG. It is a graph which shows the relationship between the Al content, the annealing temperature at a heating rate of 50 ° C./Hr, and the ferrite grain size number.
【図４】ｓｏｌ．Ａｌ量と焼鈍加熱速度とフェライト結
晶粒との関係を示す模式図である。FIG. It is a schematic diagram which shows the relationship between the amount of Al, the annealing heating rate, and a ferrite crystal grain.
Claims (1)
０５％以下、Ｐ：０．０５０％以下、Ｓ：０．０３０％
以下、Ｍｎ：０．１０〜０．４０％、ｓｏｌ．Ａｌ：
０．００５〜０．０２５％を含有し、残部がＦｅおよび
不可避的不純物からなる熱延鋼帯を、酸洗、冷間圧延し
たのち、水素濃度７５％以上の還元性雰囲気ガス中、加
熱速度３０℃／Ｈｒ以上、焼鈍温度５８０〜７００℃で
箱焼鈍することを特徴とする加工性に優れた冷延鋼帯の
製造方法。1. C: 0.02 to 0.10%, Si: 0.
05% or less, P: 0.050% or less, S: 0.030%
Hereinafter, Mn: 0.10 to 0.40%, sol. Al:
A hot-rolled steel strip containing 0.005 to 0.025%, the balance being Fe and unavoidable impurities, is pickled and cold-rolled, and then heated in a reducing atmosphere gas having a hydrogen concentration of 75% or more. A method for producing a cold-rolled steel strip excellent in workability, characterized by performing box annealing at an annealing temperature of 580 to 700 ° C at 30 ° C / Hr or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14814792A JP2705461B2 (en) | 1992-05-13 | 1992-05-13 | Method of manufacturing cold rolled steel strip with excellent workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14814792A JP2705461B2 (en) | 1992-05-13 | 1992-05-13 | Method of manufacturing cold rolled steel strip with excellent workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05311247A JPH05311247A (en) | 1993-11-22 |
| JP2705461B2 true JP2705461B2 (en) | 1998-01-28 |
Family
ID=15446319
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14814792A Expired - Fee Related JP2705461B2 (en) | 1992-05-13 | 1992-05-13 | Method of manufacturing cold rolled steel strip with excellent workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2705461B2 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100705957B1 (en) * | 2005-12-22 | 2007-04-12 | 현대하이스코 주식회사 | Tempering heat treatment cycle in the baf for producing cold rolled steel sheet having guranteed hardeness |
| KR100812051B1 (en) * | 2006-11-08 | 2008-03-10 | 현대하이스코 주식회사 | Heat treating method for high-tensile steel sheet for car use in the batch annealing furnace |
| KR101039984B1 (en) * | 2008-10-02 | 2011-06-09 | 현대하이스코 주식회사 | Batch annealing furnace heat trearment conditions for high strength steel |
| KR101033339B1 (en) * | 2011-01-04 | 2011-05-09 | 현대하이스코 주식회사 | Heat treating method for door frame steel sheet using batch annealing furnace |
| KR101033412B1 (en) * | 2011-01-04 | 2011-05-11 | 현대하이스코 주식회사 | Batch annealing furnace heat treating method of steel sheet for drum |
| CN115595503A (en) * | 2022-10-10 | 2023-01-13 | 本钢板材股份有限公司（Cn） | Hot-rolled pickled plate for high-hardness shaft net and preparation method thereof |
-
1992
- 1992-05-13 JP JP14814792A patent/JP2705461B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH05311247A (en) | 1993-11-22 |
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