JP2016141848A - Method for producing high strength steel sheet having excellent moldability - Google Patents
Method for producing high strength steel sheet having excellent moldability Download PDFInfo
- Publication number
- JP2016141848A JP2016141848A JP2015019063A JP2015019063A JP2016141848A JP 2016141848 A JP2016141848 A JP 2016141848A JP 2015019063 A JP2015019063 A JP 2015019063A JP 2015019063 A JP2015019063 A JP 2015019063A JP 2016141848 A JP2016141848 A JP 2016141848A
- Authority
- JP
- Japan
- Prior art keywords
- steel strip
- hot
- coil
- rolled steel
- 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
Images
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
Abstract
Description
本発明は、高強度鋼板を製造する方法に関するものであり、詳しくは、Mn含有量の多い高強度鋼板を製造するに際し、素材となる熱延鋼帯の全長にわたって軟質なフェライト相を主体とする金属組織を生成させることによって、熱延板焼鈍（たとえば箱焼鈍等）を施すことなく、成形性に優れた高強度鋼板を製造する方法を提案するものである。 The present invention relates to a method for producing a high-strength steel sheet. Specifically, when producing a high-strength steel sheet having a high Mn content, the main component is a soft ferrite phase over the entire length of a hot-rolled steel strip as a material. The present invention proposes a method for producing a high-strength steel sheet having excellent formability without performing hot-rolled sheet annealing (for example, box annealing) by generating a metal structure.
従来から熱間圧延においては、仕上げ圧延で所定の板厚に圧延した熱延鋼帯を、ランナウトテーブル上で冷却し、ダウンコイラでコイルに巻取っている。比較的軟質（いわゆる軟鋼等）の熱延鋼帯は、ランナウトテーブル上の冷却によって変態が完了し、フェライトとパーライトが全長にわたって生成した後に、コイルに巻取られる。その結果、コイルに巻取った熱延鋼帯から鋼板を得るために種々の加工（たとえは冷間圧延等）を施す際、組織が軟質で十分な変形能を有するため、加工が容易で、その鋼板を所定の形状（たとえば自動車の車体等）に成形するための加工（たとえば剪断、プレス等）を支障なく行なうことができる。 Conventionally, in hot rolling, a hot-rolled steel strip rolled to a predetermined thickness by finish rolling is cooled on a run-out table and wound on a coil by a downcoiler. A relatively soft (so-called mild steel, etc.) hot-rolled steel strip is wound around a coil after transformation is completed by cooling on the run-out table and ferrite and pearlite are formed over the entire length. As a result, when performing various processes (for example, cold rolling, etc.) to obtain a steel sheet from a hot-rolled steel strip wound on a coil, the structure is soft and has sufficient deformability, so the process is easy. Processing (for example, shearing, pressing, etc.) for forming the steel sheet into a predetermined shape (for example, a car body of an automobile) can be performed without any trouble.
一方で、近年、自動車用鋼板の分野では、環境保護の観点から車体の軽量化が求められている。高強度鋼板を採用すれば、自動車の車体の軽量化は可能であるが、高強度鋼板は硬質であり、成形性に関連する機械的特性（たとえば延性、伸び等）が劣るという問題がある。そこで、強度の向上と成形性の改善とを両立させた鋼板を製造する技術が検討されている。 On the other hand, in recent years, in the field of automotive steel sheets, weight reduction of vehicle bodies has been demanded from the viewpoint of environmental protection. If a high-strength steel plate is used, the weight of the automobile body can be reduced, but the high-strength steel plate is hard and has a problem that mechanical properties related to formability (for example, ductility, elongation, etc.) are inferior. Therefore, a technique for producing a steel sheet that achieves both improvement in strength and improvement in formability has been studied.
たとえば特許文献１には、C、Si、Mn等の元素を多量に添加して、成形性に優れた高強度鋼板を得る技術が開示されている。しかし、これらの元素、とりわけMnは、フェライト変態を遅延させる作用を有しているので、熱延鋼帯をランナウトテーブル上で冷却してコイルに巻取るときには、フェライト変態がほとんど生じておらず、そのコイルをコイルヤードに保管する間に、温度が低下することによって様々な変態が進行する。特に、コイルの内周部（すなわち熱延鋼帯の先端部）と外周部（すなわち熱延鋼帯の尾端部）は、冷却速度が大きくなるので、Mnを多量に含有する熱延鋼帯は、フェライト変態が進行せず、硬質の金属組織が生成し易い。その結果、冷間圧延における荷重が増大し、圧延速度の低下、ひいては生産性の低下を招く。さらに、コイルの巻き周期に応じた硬さ変動が生じて、寸法精度や機械的特性の劣る部位が発生し、歩留りの低下を招く惧れもある。
For example,
このような問題を解消するためには、コイルに巻取られた熱延鋼帯の全長にわたって軟質な金属組織を均一に生成させる必要がある。冷間圧延する前のコイルに箱焼鈍を施すことによって、熱延鋼帯の組織の軟質化を図ることは可能であるが、高強度鋼板の製造コストの上昇のみならず、表面性状の劣化を招く。しかも、熱延鋼帯が脆化して、冷間圧延にて破断し易くなるという問題が生じる。そこで、巻取った後の冷却過程で様々な処置を施すことによって、コイルに箱焼鈍を施すことなく、熱延鋼帯に好適な金属組織を生成させる技術が検討されている。 In order to solve such a problem, it is necessary to uniformly generate a soft metal structure over the entire length of the hot-rolled steel strip wound around the coil. By subjecting the coil before cold rolling to box annealing, it is possible to soften the structure of the hot-rolled steel strip, but not only increase the manufacturing cost of high-strength steel sheets, but also deteriorate the surface properties. Invite. In addition, the hot-rolled steel strip becomes brittle and is likely to break by cold rolling. Then, the technique of producing | generating the metal structure suitable for a hot-rolled steel strip is examined without giving box annealing to a coil by giving various treatments in the cooling process after winding.
たとえば特許文献２には、熱延鋼帯をコイルに巻取った後に、そのコイルの搬送装置や保管場所にてコイルの内周部や外周部に接触する部分を加熱する、あるいは接触しない部分を冷却することによって、フェライトを生成させ得る冷却速度を保持する技術が開示されている。この技術は、局所的な加熱あるいは冷却を行なう装置が必要であり、かつ燃料消費量が増加するので、高強度鋼板の製造コストの増大を招く。さらに、局所的な加熱、冷却に起因する機械的特性の変動が生じる惧れもある。 For example, in Patent Document 2, after winding a hot-rolled steel strip around a coil, a portion that is in contact with the inner peripheral portion or the outer peripheral portion of the coil is heated or not in contact with the conveying device or storage location of the coil. A technique for maintaining a cooling rate capable of generating ferrite by cooling is disclosed. This technique requires a device that performs local heating or cooling, and increases the fuel consumption, leading to an increase in the manufacturing cost of the high-strength steel sheet. Furthermore, there is a possibility that fluctuations in mechanical properties due to local heating and cooling occur.
さらに特許文献３には、830〜950℃の範囲で熱間圧延を行ない、次いで650℃まで平均20〜90℃／秒の冷却速度で冷却し、その後、470〜640℃の温度域まで平均５〜30℃／秒の冷却速度で冷却してコイルに巻取ることによって、フェライトとパーライトを生成させる技術が開示されている。この技術は、上記の冷却速度をランナウトテーブル上で確保するために、仕上げ圧延から巻取りまでの所要時間を延長せざるを得ないので、粗圧延から仕上げ圧延を経て巻取りに至る一連の熱間圧延の操業に適用することは困難である。また、上記の冷却速度を確保しつつ操業を行なえば、熱延鋼帯の生産性の低下、ひいては高強度鋼板の生産性の低下を招く。 Furthermore, in Patent Document 3, hot rolling is performed in the range of 830 to 950 ° C., and then cooling is performed at an average cooling rate of 20 to 90 ° C./second up to 650 ° C., and then an average of 5 to a temperature range of 470 to 640 ° C. A technique for generating ferrite and pearlite by cooling at a cooling rate of ˜30 ° C./second and winding on a coil is disclosed. In this technology, in order to secure the above cooling rate on the run-out table, the time required from finish rolling to winding must be extended, so a series of heat from rough rolling to finishing rolling to winding. It is difficult to apply to hot rolling operations. Further, if the operation is performed while ensuring the above cooling rate, the productivity of the hot-rolled steel strip is lowered, and consequently the productivity of the high-strength steel plate is lowered.
特許文献４には、熱延鋼帯の先端部を冷却し、中央部や尾端部の温度よりも40〜80℃低下させてコイルに巻取る技術が開示されている。この技術は、熱延鋼帯を巻取る際に、その先端部がマンドレルに接触して冷却され、その結果、先端部の機械的特性が変動するのを防止するものである。この技術は、巻取りを開始する時の局所的な冷却を緩和するものであり、熱延鋼帯をコイルに巻取った後の冷却過程で尾端部に生じる変態を制御することは困難である。 Patent Document 4 discloses a technique in which the tip of a hot-rolled steel strip is cooled and wound around a coil at a temperature lower by 40 to 80 ° C. than the temperature at the center or tail. In this technique, when the hot-rolled steel strip is wound, the tip portion thereof contacts the mandrel and is cooled, and as a result, the mechanical properties of the tip portion are prevented from fluctuating. This technology alleviates local cooling when starting winding, and it is difficult to control the transformation that occurs at the tail end during the cooling process after winding the hot-rolled steel strip around the coil. is there.
本発明は、従来の技術の問題点を解消し、Mn含有量の多い熱延鋼帯をコイルに巻取った後の冷却過程における変態を制御することによって、コイルに箱焼鈍を施すことなく、熱延鋼帯の全長にわたって軟質な金属組織（すなわちフェライトの単相組織またはフェライトとパーライトとの混合組織）を均一に生成させ、次いで、その熱延鋼帯に冷間圧延等を施して、成形性に優れた高強度鋼板を製造する方法を提供することを目的とする。 The present invention eliminates the problems of the prior art and controls the transformation in the cooling process after winding a hot rolled steel strip with a high Mn content on the coil, without subjecting the coil to box annealing, Form a soft metal structure (ie, a single phase structure of ferrite or a mixed structure of ferrite and pearlite) uniformly over the entire length of the hot-rolled steel strip, and then cold-roll the hot-rolled steel strip to form It aims at providing the method of manufacturing the high strength steel plate excellent in property.
本発明者は、Mn含有量の多い熱延鋼帯の全長にわたって軟質な金属組織を均一に生成させる技術を検討するにあたって、熱延鋼帯を巻取ったコイルの内周部と外周部の冷却速度が、中央部よりも大きくなる点に着目した。つまり、コイルの内周部と外周部は大気と接触する面積が広いので、放散される熱量が増加して、冷却速度が大きくなる。この冷却速度の相違は、冷却した後の金属組織が不均一に生成される原因となる。 In examining the technology for uniformly generating a soft metal structure over the entire length of a hot rolled steel strip having a high Mn content, the inventor cooled the inner and outer peripheral portions of a coil wound with the hot rolled steel strip. We paid attention to the fact that the speed was larger than the central part. That is, since the inner and outer peripheral portions of the coil have a large area in contact with the atmosphere, the amount of heat dissipated increases and the cooling rate increases. This difference in cooling rate causes the metal structure after cooling to be generated unevenly.
そして、コイルの内周部と外周部の温度履歴、および中央部の温度履歴を調整して、フェライト変態を均一に進行させる技術について詳細に研究した。その結果、熱延鋼帯の素材となる鋼スラブの成分を適正に設計するとともに、熱延鋼帯をコイルに巻取る前に、熱延鋼帯の先端部（すなわちコイルの内周側に位置する部位）の温度と、熱延鋼帯の尾端部（すなわちコイルの外周側に位置する部位）の温度と、を予め上昇させておき、中央部の温度よりも高くして巻取り、さらに保熱しながら冷却することによって、巻取った後の熱延鋼帯の全長にわたって均一なフェライト変態を生じさせることが可能となることを見出した。 Then, the temperature history of the inner and outer peripheral portions of the coil and the temperature history of the central portion were adjusted to study in detail the technology for causing the ferrite transformation to proceed uniformly. As a result, the components of the steel slab, which is the material of the hot-rolled steel strip, are designed appropriately, and before the hot-rolled steel strip is wound around the coil, the tip of the hot-rolled steel strip (that is, located on the inner peripheral side of the coil) ) And the temperature of the tail end portion of the hot-rolled steel strip (that is, the portion located on the outer peripheral side of the coil) are raised in advance, wound higher than the temperature of the central portion, It has been found that by cooling while keeping heat, a uniform ferrite transformation can be generated over the entire length of the hot-rolled steel strip after winding.
さらに、その後の酸洗、冷間圧延、焼鈍を通常の設定条件で行なうことによって、高強度鋼板の脆化を抑え、優れた成形性が得られることが分かった。 Furthermore, it was found that by performing subsequent pickling, cold rolling, and annealing under normal setting conditions, embrittlement of the high-strength steel sheet can be suppressed and excellent formability can be obtained.
本発明は、このような知見に基づいてなされたものである。 The present invention has been made based on such knowledge.
すなわち本発明は、C：0.03〜0.25質量％、Si：0.01〜3.0質量％、Mn：3.1〜5.1質量％、P：0.10質量％以下、S：0.02質量％以下を含有し、残部がFeおよび不可避的不純物からなる鋼スラブを熱間圧延して熱延鋼帯とし、熱延鋼帯を巻取ってコイルとした後に、コイルを冷却し、次いでコイルに巻取られた熱延鋼帯に酸洗、冷間圧延、焼鈍を施す成形性に優れた高強度鋼板の製造方法において、熱間圧延で得られた熱延鋼帯をコイルに巻取る際に、コイルの冷却速度の大きい内周部と外周部に相当する熱延鋼帯の先端部と尾端部の巻取り温度を高くし、かつコイルの冷却速度の小さい中間部に相当する熱延鋼帯の中央部の巻取り温度を低くして巻取ることによってコイルとし、さらに得られたコイルを保熱手段または加熱手段に収納して500℃以上の温度域で50時間以上保持した後に、冷却を行なう成形性に優れた高強度鋼板の製造方法である。 That is, the present invention contains C: 0.03-0.25 mass%, Si: 0.01-3.0 mass%, Mn: 3.1-5.1 mass%, P: 0.10 mass% or less, S: 0.02 mass% or less, with the balance being Fe and A steel slab made of unavoidable impurities is hot-rolled to form a hot-rolled steel strip, the hot-rolled steel strip is wound into a coil, the coil is cooled, and then the hot-rolled steel strip wound on the coil is acidified. In the manufacturing method of high-strength steel sheet with excellent formability that is washed, cold-rolled, and annealed, when the hot-rolled steel strip obtained by hot rolling is wound around the coil, the inner peripheral part where the coil cooling rate is large And increase the coiling temperature at the tip and tail ends of the hot-rolled steel strip corresponding to the outer periphery, and lower the coiling temperature at the center of the hot-rolled steel strip corresponding to the intermediate portion where the coil cooling rate is small. And then coiled into a coil, and the obtained coil is housed in a heat retaining means or a heating means and a temperature range of 500 ° C. or higher. After holding 50 hours, the method of producing a high strength steel sheet excellent in formability for cooling.
本発明の高強度鋼板の製造方法においては、熱延鋼帯の先端から鋼帯全長の20％以内の範囲および尾端から鋼帯全長の30％以内の範囲の巻取り温度を600℃以上とし、熱延鋼帯の長手方向の中央から前方に鋼帯全長の25％以内および後方に鋼帯全長の25％以内の範囲の巻取り温度を530〜570℃となるように熱延鋼帯の長手方向の温度分布を調整してコイルに巻取ることが好ましい。 In the method for producing a high-strength steel sheet of the present invention, the coiling temperature in the range within 20% of the total length of the steel strip from the tip of the hot-rolled steel strip and in the range of within 30% of the total length of the steel strip is set to 600 ° C or higher. The hot-rolled steel strip has a coiling temperature of 530 to 570 ° C within a range of 25% of the total length of the steel strip from the center to the front in the longitudinal direction of the hot-rolled steel strip and within 25% of the total length of the steel strip. It is preferable to adjust the temperature distribution in the longitudinal direction to wind the coil.
本発明によれば、Mn含有量の多い熱延鋼帯を巻取ったコイルに箱焼鈍を施すことなく、熱延鋼帯の全長にわたってフェライトの単相組織またはフェライトとパーライトとの混合組織を生成させることができ、その結果、熱延鋼帯に通常の設定条件で冷間圧延等を施して成形性に優れた高強度鋼板を得ることが可能となるので、産業上格段の効果を奏する。 According to the present invention, a single-phase structure of ferrite or a mixed structure of ferrite and pearlite is generated over the entire length of the hot-rolled steel strip without subjecting the coil wound with the hot-rolled steel strip having a high Mn content to box annealing. As a result, it is possible to obtain a high-strength steel sheet having excellent formability by subjecting the hot-rolled steel strip to cold rolling or the like under normal setting conditions, and thus has a remarkable industrial effect.
まず、本願発明に係る熱延鋼帯の素材となる鋼スラブの成分について説明する。
C：0.03〜0.25質量％
Cは、熱延鋼帯の強度、ひいては高強度鋼板の強度を高めるとともに、残留オーステナイトを生成させて、伸びを向上する作用を有する元素である。C含有量が0.03質量％未満では、強度と伸びを向上させる効果が得られない。一方で、0.25質量％を超えると、高強度鋼板の溶接性が著しく劣化する。したがって、Cは0.03〜0.25質量％の範囲内とする。
First, the components of the steel slab that is the material of the hot-rolled steel strip according to the present invention will be described.
C: 0.03-0.25 mass%
C is an element that has the action of increasing the strength of the hot-rolled steel strip, and consequently the strength of the high-strength steel sheet, and generating retained austenite to improve elongation. If the C content is less than 0.03% by mass, the effect of improving strength and elongation cannot be obtained. On the other hand, if it exceeds 0.25% by mass, the weldability of the high-strength steel sheet is significantly deteriorated. Therefore, C is in the range of 0.03 to 0.25 mass%.
Si：0.01〜3.0質量％
Siは、Cと同様に、熱延鋼帯の強度、ひいては高強度鋼板の強度を高めるとともに、高強度鋼板の加工性の向上に寄与する元素である。Si含有量が0.01質量％未満では、その効果が得られない。一方で、3.0質量％を超えると、赤スケール等の発生に起因する表面性状の劣化を引き起こすばかりでなく、化成処理やめっきに悪影響を及ぼす。したがって、Siは0.01〜3.0質量％の範囲内とする。
Si: 0.01-3.0 mass%
Si, like C, is an element that contributes to improving the workability of a high-strength steel sheet as well as increasing the strength of the hot-rolled steel strip and thus the strength of the high-strength steel sheet. If the Si content is less than 0.01% by mass, the effect cannot be obtained. On the other hand, if it exceeds 3.0% by mass, it not only causes deterioration of the surface properties due to the occurrence of red scale and the like, but also adversely affects chemical conversion treatment and plating. Therefore, Si is in the range of 0.01 to 3.0 mass%.
Mn：3.1〜5.1質量％
Mnは、熱延鋼帯の強度、ひいては高強度鋼板の強度を高める作用を有し、かつＣＣＴ線図やＴＴＴ線図におけるフェライトノーズの位置を大きく変動させるので、重要な元素である。Mn含有量が3.1質量％未満では、十分な強度が得られず、また、熱延鋼帯のコイルを保熱することにより、フェライト変態が進行し、コイル全長にわたって均質なフェライト組織が生成される。これは、Mn含有量が3.1質量％未満の熱延鋼帯に本発明を適用する必要がないことを意味する。一方で、5.1質量％を超えると、本発明を適用して熱延鋼帯の長手方向の温度分布を調整しても、コイルの冷却過程でフェライト変態が生じない。したがって、Mnは3.1〜5.1質量％の範囲内とする。
なお、ＣＣＴ線図とＴＴＴ線図については後述する。
Mn: 3.1-5.1% by mass
Mn is an important element because it has the effect of increasing the strength of the hot-rolled steel strip, and consequently the strength of the high-strength steel plate, and greatly fluctuates the position of the ferrite nose in the CCT diagram and TTT diagram. When the Mn content is less than 3.1% by mass, sufficient strength cannot be obtained, and by keeping the coil of the hot-rolled steel strip, the ferrite transformation proceeds and a homogeneous ferrite structure is generated over the entire length of the coil. . This means that it is not necessary to apply the present invention to a hot-rolled steel strip having an Mn content of less than 3.1% by mass. On the other hand, if it exceeds 5.1% by mass, ferrite transformation does not occur in the cooling process of the coil even if the temperature distribution in the longitudinal direction of the hot-rolled steel strip is adjusted by applying the present invention. Therefore, Mn is in the range of 3.1 to 5.1 mass%.
The CCT diagram and the TTT diagram will be described later.
P：0.10質量％以下
Pは、溶接性や靭性に悪影響を及ぼす元素であり、P含有量が0.10質量％を超えると、高強度鋼板の靭性が低下するばかりでなく、溶接性も劣化する。したがって、Pは0.10質量％以下とする。
P: 0.10% by mass or less
P is an element that adversely affects weldability and toughness. When the P content exceeds 0.10% by mass, not only the toughness of the high-strength steel sheet decreases, but also the weldability deteriorates. Therefore, P is 0.10% by mass or less.
S：0.02質量％以下
Sは、伸びフランジ性や靭性に悪影響を及ぼす元素である。そのためSはできるだけ低減することが好ましいが、過度の低減は熱延鋼帯の製造コスト、ひいては高強度鋼板の製造コストの増大を招く。したがって、Sは0.02質量％以下とする。
S: 0.02 mass% or less
S is an element that adversely affects stretch flangeability and toughness. Therefore, it is preferable to reduce S as much as possible. However, excessive reduction leads to an increase in the manufacturing cost of the hot-rolled steel strip, and hence the manufacturing cost of the high-strength steel plate. Therefore, S is 0.02 mass% or less.
さらに本願発明に係る熱延鋼帯は、AlとNを下記の範囲で含有しても良い。 Furthermore, the hot-rolled steel strip according to the present invention may contain Al and N in the following ranges.
Al：0.02〜0.1質量％
Alは、脱酸剤として溶鋼の溶製工程で添加する元素であるが、その脱酸作用のみならず、AlNを形成して、高温で結晶粒が粗大に成長するのを抑制する作用も有する。Al含有量が0.02質量％未満では、この効果が得られない。一方で、0.1質量％を超えると、溶鋼の清浄度が低下する。したがって、Alは0.02〜0.1質量％の範囲内が好ましい。
Al: 0.02 to 0.1% by mass
Al is an element that is added as a deoxidizer in the melting process of molten steel. Not only its deoxidizing action, but also has the action of forming AlN and suppressing the coarse growth of crystal grains at high temperatures. . If the Al content is less than 0.02% by mass, this effect cannot be obtained. On the other hand, if it exceeds 0.1% by mass, the cleanliness of the molten steel decreases. Therefore, Al is preferably in the range of 0.02 to 0.1% by mass.
N：0.008質量％以下
Nは、Alと結合してAlNを形成し、結晶粒の粗大化を抑制する作用を有するので、適量を含有させることが好ましい。ただしN含有量が0.008質量％を超えると、高強度鋼板の溶接性が低下する。したがって、Nは0.008質量％以下が好ましい。
N: 0.008% by mass or less
N binds to Al to form AlN and has an action of suppressing the coarsening of crystal grains, and therefore it is preferable to contain an appropriate amount. However, when N content exceeds 0.008 mass%, the weldability of a high-strength steel plate will fall. Therefore, N is preferably 0.008% by mass or less.
また、強度と成形性を一層高めるために、Nb、Ti、Vを含有させても良い。Nb、Ti、Vは、いずれも炭窒化物を形成し、析出強化によって高強度鋼板の強度の向上に寄与する元素である。このような効果を得るためには、いずれも0.005質量％以上を含有させることが好ましい。一方で、いずれの元素も0.15質量％を超えて含有しても効果が飽和して、含有量に見合う効果が期待できなくなる。その結果、製造コストの増大を招く。したがってNb、Ti、Vを含有させる場合は、各元素の含有量をそれぞれ0.005〜0.15質量％の範囲内とすることが好ましい。そしてNb、Ti、Vの中から、必要に応じて１種または２種以上を選択して含有させることが好ましい。 Further, Nb, Ti, and V may be contained in order to further increase the strength and formability. Nb, Ti, and V are all elements that form carbonitrides and contribute to improving the strength of high-strength steel sheets by precipitation strengthening. In order to acquire such an effect, it is preferable to contain 0.005 mass% or more in any case. On the other hand, even if any element exceeds 0.15% by mass, the effect is saturated and an effect commensurate with the content cannot be expected. As a result, the manufacturing cost increases. Therefore, when Nb, Ti, and V are contained, the content of each element is preferably within the range of 0.005 to 0.15 mass%. And it is preferable to select 1 type or 2 types or more from Nb, Ti, and V as needed.
これらの元素に加えて、Cr、Ni、Cu、Mo、B、Ca等、必要な元素を含有させることは、本発明の効果を何ら妨げるものではなく、その含有量は適宜設定すれば良い。
上記した成分以外は、Feおよび不可避的不純物である。
In addition to these elements, inclusion of necessary elements such as Cr, Ni, Cu, Mo, B, and Ca does not hinder the effects of the present invention at all, and the content thereof may be set as appropriate.
Other than the above-described components, Fe and unavoidable impurities.
ここで、ＣＣＴ線図とＴＴＴ線図について説明する。
仕上げ圧延した後の熱延鋼帯をランナウトテーブル上で冷却する、あるいはコイルに巻取った後に冷却する過程における変態挙動を予測し、それに基づいて、室温まで冷却して得られる金属組織を予測するために、ＣＣＴ線図（連続冷却変態線図）やＴＴＴ線図（恒温変態曲線図）が広く用いられている。ＣＣＴ線図は、所定の成分の鋼をオーステナイト域から種々の冷却速度で連続冷却してフェライトに変態する温度と時刻を図示するものであり、ＴＴＴ線図は、オーステナイト域から所定の温度まで冷却した後、その温度で保持し、フェライト変態の開始までの時間を図示したものである。
Here, the CCT diagram and the TTT diagram will be described.
Predict the transformation behavior in the process of cooling the hot-rolled steel strip after finish rolling on a run-out table or cooling it after winding it on a coil, and predict the metal structure obtained by cooling to room temperature based on it Therefore, a CCT diagram (continuous cooling transformation diagram) and a TTT diagram (constant temperature transformation curve diagram) are widely used. The CCT diagram illustrates the temperature and time at which the steel of a predetermined component is continuously cooled from the austenite region at various cooling rates to transform into ferrite, and the TTT diagram is cooled from the austenite region to the predetermined temperature. Then, the temperature is maintained at that temperature, and the time until the start of the ferrite transformation is illustrated.
本発明に係る熱延鋼帯はMnを多量に含有しているので、ＣＣＴ線図やＴＴＴ線図におけるフェライトノーズが、一般の熱延鋼帯よりも長時間側（すなわち103〜105秒）に存在する。 Since the hot-rolled steel strip according to the present invention contains a large amount of Mn, the ferrite nose in the CCT diagram or TTT diagram is longer than the general hot-rolled steel strip (that is, 10 3 to 10 5 seconds). ).
熱延鋼帯は、コイルに巻き取った後に空冷されるので、大気に接触するコイルの内周部および外周部の冷却速度は大きくなり、短時間で温度が低下する。一方、コイルの中央部は大気にほとんど接触しないので、冷却速度は小さくなり、冷却に長時間を要する。つまり、コイルの内周部は熱延鋼帯の先端部に相当し、コイルの外周部は熱延鋼帯の尾端部に相当することから、熱延鋼帯の先端部、尾端部、中央部の温度履歴に差異が生じ、その結果、熱延鋼帯の成分により、熱延鋼帯の長手方向で異なる金属組織が生成される。 Since the hot-rolled steel strip is air-cooled after being wound around the coil, the cooling rate of the inner and outer peripheral portions of the coil that comes into contact with the air increases, and the temperature decreases in a short time. On the other hand, since the central portion of the coil hardly comes into contact with the atmosphere, the cooling rate becomes small and it takes a long time for cooling. That is, since the inner peripheral portion of the coil corresponds to the tip portion of the hot-rolled steel strip, and the outer peripheral portion of the coil corresponds to the tail end portion of the hot-rolled steel strip, the tip portion of the hot-rolled steel strip, the tail end portion, A difference occurs in the temperature history of the central portion, and as a result, different metal structures are generated in the longitudinal direction of the hot-rolled steel strip due to the components of the hot-rolled steel strip.
図１は、熱延鋼帯を巻取ったコイル（巻取り温度620℃）を空冷する際の、コイルの外周部の温度推移を示す曲線（以下、温度履歴という）TE（計算結果）、コイルの中央部の温度履歴MID（計算結果）と、フェライトノーズαSとの関係の一例を示すグラフである。なおコイルの内周部の温度履歴は、図１中のTEとほぼ同等であるから、図示を省略する。 Fig. 1 shows a curve (hereinafter referred to as temperature history) TE (calculation result) TE (calculation result), coil showing the temperature transition of the outer periphery of the coil when the coil wound with a hot-rolled steel strip (winding temperature 620 ° C) is air-cooled. 6 is a graph showing an example of the relationship between the temperature history MID (calculation result) in the center of the ferrite nose α S. Note that the temperature history of the inner peripheral portion of the coil is substantially the same as TE in FIG.
図１に示すように、フェライトノーズが103〜104秒の範囲に存在する場合は、温度履歴の差異に起因して、コイルの内周部と外周部に生成する金属組織は、中央部に生成する金属組織と相違する。したがって熱延鋼帯の長手方向に異なる金属組織が生成し、機械的特性（たとえば強度、伸び等）や寸法、表面性状が変動するので、高強度鋼板を加工して製造する最終製品（たとえば自動車の車体等）の歩留りが低下する。 As shown in FIG. 1, when the ferrite nose is present in the range of 10 3 to 10 4 seconds, the metal structure generated in the inner and outer peripheral portions of the coil is caused by the difference in temperature history. It differs from the metallographic structure produced in Therefore, different metal structures are formed in the longitudinal direction of the hot-rolled steel strip, and mechanical properties (for example, strength, elongation, etc.), dimensions, and surface properties vary, so that the final product (for example, an automobile) manufactured by processing a high-strength steel sheet The yield of the vehicle body, etc.) decreases.
熱延鋼帯の中央部の巻取り温度を強制的に低下させれば、機械的特性が長手方向に変動するのを抑制することは可能であるが、硬質な金属組織が生成されるので、冷間圧延における圧延荷重の増加等の問題が生じる。これに対して、熱延鋼帯を全長にわたってフェライトを主相とする軟質な金属組織とすれば、冷間圧延を支障なく行なうことができる。 If the coiling temperature at the center of the hot-rolled steel strip is forcibly lowered, it is possible to suppress the mechanical properties from fluctuating in the longitudinal direction, but a hard metal structure is generated. Problems such as an increase in rolling load in cold rolling occur. On the other hand, if the hot-rolled steel strip has a soft metal structure with ferrite as the main phase over the entire length, cold rolling can be performed without hindrance.
次に、フェライトを主相とする軟質な金属組織を得るために好適な、温度履歴とフェライトノーズの関係について説明する。 Next, the relationship between temperature history and ferrite nose, which is suitable for obtaining a soft metal structure having ferrite as a main phase, will be described.
Mn含有量の変化に起因するフェライトノーズの位置の変動を調査するために、表１に示す成分の鋼スラブ（鋼記号Ａ〜Ｃ）を、1000℃で均熱（２時間）した後に、950℃で圧延（総圧下率70％）して熱延鋼帯とし、さらにコイルに巻取った。引き続きそのコイルを550〜650℃で保熱（１〜100時間）した後に、空冷して室温まで冷却した。そして、得られた金属組織を調査して、フェライトノーズの位置を推定した。その結果を図２に示す。図２中のコイルの外周部の温度履歴TEと中央部の温度履歴MIDは図１と同じである。 In order to investigate the variation in the position of the ferrite nose due to the change in the Mn content, the steel slabs (steel symbols A to C) having the components shown in Table 1 were soaked at 1000 ° C. (2 hours), then 950 It was rolled at 70 ° C. (total rolling reduction of 70%) to form a hot-rolled steel strip, and further wound on a coil. Subsequently, the coil was kept at 550 to 650 ° C. (1 to 100 hours) and then cooled to room temperature by air cooling. And the obtained metal structure was investigated and the position of the ferrite nose was estimated. The result is shown in FIG. The temperature history TE at the outer periphery of the coil and the temperature history MID at the center in FIG. 2 are the same as those in FIG.
図２に示す通り、Mn含有量が2.9質量％の鋼記号Ａでは、フェライトノーズは104秒より短時間側に存在し、Mn含有量が3.2質量％の鋼記号Ｂでは、フェライトノーズは104〜105秒の範囲、Mn含有量が4.4質量％の鋼記号Ｃでは、フェライトノーズは105秒より長時間側に存在する。 As shown in FIG. 2, the Mn content is 2.9 mass% of the steel symbols A, ferrite nose is present a short time side of 10 4 seconds, the Mn content is 3.2 mass% of the steel symbol B, the ferrite nose 10 In the steel code C having a Mn content of 4.4 mass% in the range of 4 to 10 5 seconds, the ferrite nose exists on the longer side than 10 5 seconds.
図３は、熱延鋼帯を巻取ったコイル（巻取り温度620℃）を保熱カバー内に収納して、保熱しながら冷却する際の、コイルの外周部の温度履歴te（計算結果）、中央部の温度履歴mid（計算結果）と、を示すグラフである。なお内周部の温度履歴は、図３中のteとほぼ同等であるから、図示を省略する。また、図３中のコイルの外周部の温度履歴TEと中央部の温度履歴MIDは図１と同じである。 Fig. 3 shows the temperature history te (calculation result) of the outer periphery of the coil when the coil (winding temperature 620 ° C) wound with the hot-rolled steel strip is housed in the heat insulating cover and cooled while heat is retained. 4 is a graph showing a temperature history mid (calculation result) in the central part. The temperature history of the inner peripheral portion is substantially the same as te in FIG. Further, the temperature history TE at the outer peripheral portion of the coil and the temperature history MID at the central portion in FIG. 3 are the same as those in FIG.
図３に示す通り、コイルを空冷する場合は、103秒程度までコイルの全長の温度を巻取り温度（620℃）−50℃の範囲に維持できることが分かる（温度履歴TEおよびMID参照）。これに対して、保熱カバーを用いて保熱しながら冷却する場合は、105秒程度までコイルの全長の温度を巻取り温度（620℃）−50℃の範囲に維持できる（温度履歴teおよびmid参照）。 As shown in FIG. 3, if the air-cooling the coil, it can be seen that maintained in the range of temperature of the overall length of the coil winding temperature (620 ° C.) -50 ° C. to about 10 3 seconds (see temperature history TE and MID). In contrast, when cooling while heating coercive using heat-retaining cover 10 up to about 5 seconds the temperature of the entire length of the coil winding temperature (620 ° C.) can be maintained in the range of -50 ° C. (temperature history te and mid).
つまり、Mn含有量が小さく、103秒程度でフェライト変態が生じる成分の熱延鋼帯は、コイルを空冷することによって、全長にわたってフェライト変態させることが可能であるから、本発明を適用する必要はない。一方、Mn含有量が大きく、フェライトノーズが104〜105秒の範囲となる成分の熱延鋼帯は、空冷によって全長にわたってフェライト変態を生じさせることが困難であるから、コイルを保熱手段（たとえば保熱カバー等）あるいは加熱手段（たとえば電気炉、ガス燃焼炉等）に収納して、保熱した後に冷却することが好ましい。保熱して温度履歴とフェライトノーズの関係を調整することによって、全長にわたってフェライト変態を生じさせることが可能となる。 In other words, small Mn content, the hot rolled steel strip of component ferrite transformation occurs in about 10 3 seconds, by cooling the coil, because it is possible to ferrite transformation over the entire length, necessary to apply the present invention There is no. On the other hand, the hot-rolled steel strip with a high Mn content and a ferrite nose in the range of 10 4 to 10 5 seconds is difficult to cause ferrite transformation over the entire length by air cooling. It is preferable to cool it after storing it in a heating means (for example, a heat retaining cover) or a heating means (for example, an electric furnace, a gas combustion furnace, etc.). By maintaining the heat and adjusting the relationship between the temperature history and the ferrite nose, it becomes possible to cause ferrite transformation over the entire length.
保熱手段としての保熱カバーは、内壁を低輻射材と耐火物で覆うことが好ましい。また、コイルを１個ずつカバーする寸法にしても良いし、あるいは複数のコイル（10〜40個程度）をまとめてカバーする寸法にしても良い。 The heat insulating cover as the heat insulating means preferably covers the inner wall with a low radiation material and a refractory. Further, the dimensions may be such that each coil is covered one by one, or a plurality of coils (about 10 to 40) may be collectively covered.
図４は、熱延鋼帯を巻取ったコイル（巻取り温度620℃）を電気炉内に収納して、加熱した後に冷却する際の、コイルの外周部の温度履歴te（計算結果）、中央部の温度履歴mid（計算結果）と、を示すグラフである。なお内周部の温度履歴は、図４中のteとほぼ同等であるから、図示を省略する。また、図４中のコイルの外周部の温度履歴TEと中央部の温度履歴MIDは図１と同じである。 FIG. 4 shows the temperature history te (calculation result) of the outer periphery of the coil when the coil (winding temperature 620 ° C.) wound around the hot-rolled steel strip is housed in an electric furnace and cooled after being heated. It is a graph which shows the temperature history mid (calculation result) of the center part. The temperature history of the inner peripheral portion is substantially the same as te in FIG. Further, the temperature history TE at the outer peripheral portion of the coil and the temperature history MID at the central portion in FIG. 4 are the same as those in FIG.
加熱手段としての電気炉やガス燃焼炉は、コイルの外周のみならず内周からも加熱できる構成が好ましい。熱源から供給される熱量等の設定は、コイルの温度を測定しながら、適宜調整すれば良い。また、コイルを１個ずつカバーする寸法にしても良いし、あるいは複数のコイル（10〜40個程度）をまとめてカバーする寸法にしても良い。 The electric furnace or gas combustion furnace as the heating means is preferably configured to be heated not only from the outer periphery of the coil but also from the inner periphery. Settings such as the amount of heat supplied from the heat source may be adjusted as appropriate while measuring the temperature of the coil. Further, the dimensions may be such that each coil is covered one by one, or a plurality of coils (about 10 to 40) may be collectively covered.
次に、熱延鋼帯の巻取り温度について説明する。
本発明は、既に述べた通り、熱延鋼帯の全長にわたってフェライト変態を生じさせるために、コイルを保熱しながら冷却するものであるから、室温に冷却されるまでに長時間を要する。そのため巻取り温度によっては、内部酸化が生じて、表面性状が劣化し、化成処理やめっきに悪影響を及ぼすという問題が生じる惧れがある。そこで、熱延鋼帯を種々の温度で保持して、内部酸化の進行状況（すなわち酸化層の厚み）を調査した。その結果、熱延鋼帯の温度が570℃以下であれば、105秒保持しても内部酸化は発生せず、600℃以上になると、104秒保持すると内部酸化が顕著に現われることが分かった。
Next, the winding temperature of the hot rolled steel strip will be described.
As described above, the present invention cools the coil while keeping the heat in order to cause the ferrite transformation over the entire length of the hot-rolled steel strip, so it takes a long time to cool to room temperature. Therefore, depending on the coiling temperature, internal oxidation may occur, the surface properties may deteriorate, and there may be a problem that the chemical conversion treatment and plating are adversely affected. Therefore, the hot-rolled steel strip was held at various temperatures, and the progress of internal oxidation (that is, the thickness of the oxide layer) was investigated. As a result, if the following temperature 570 ° C. of the hot rolled strip, 10 be 5 seconds hold internal oxidation does not occur, becomes more than 600 ° C., that the internal oxidation Holding 10 4 seconds appears conspicuously I understood.
ところで、熱延鋼帯をコイルに巻取った後、保熱あるいは加熱を施すまでに、コイルのハンドリングや搬送に10分程度を要する。そのため、熱延鋼帯の巻取り温度を、たとえば570℃に設定すると、コイルの内周部と外周部の温度は520℃程度に低下し、その温度から保熱しながら冷却、あるいは加熱した後に冷却しても、フェライト変態は生じない。また、熱延鋼帯の巻取り温度を、たとえば620℃に設定すると、コイルの内周部と外周部の温度は570℃程度に保熱されてフェライト変態が生じるが、中央部は長時間620℃に保持されるので内部酸化が生じる。 By the way, after the hot-rolled steel strip is wound around the coil, it takes about 10 minutes to handle and carry the coil before heat retention or heating. Therefore, if the coiling temperature of the hot-rolled steel strip is set to, for example, 570 ° C., the temperature of the inner and outer peripheral portions of the coil is lowered to about 520 ° C. Even so, ferrite transformation does not occur. If the coiling temperature of the hot-rolled steel strip is set to 620 ° C., for example, the temperature of the inner and outer peripheral portions of the coil is kept at about 570 ° C. and ferrite transformation occurs, but the central portion has a long time of 620 ° C. Internal oxidation occurs because it is maintained at ° C.
そこで、熱延鋼帯の先端部と尾端部の巻取り温度を高く設定し、中央部の巻取り温度を低く設定する。具体的には、熱延鋼帯の先端部の巻取り温度ＴTと尾端部の巻取り温度ＴBを600℃以上とし、中央部の巻取り温度ＴCを530〜570℃とすることが好ましい。ここで、熱延鋼帯の先端部は熱延鋼帯の先端から鋼帯全長の20％以内の範囲、尾端部は熱延鋼帯の尾端から鋼帯全長の30％以内の範囲、中央部は熱延鋼帯の長手方向の中央から前方に鋼帯全長の25％以内および後方に鋼帯全長の25％以内の範囲（合計50％以内）とする。 Therefore, the winding temperature at the tip and tail ends of the hot-rolled steel strip is set high, and the winding temperature at the center is set low. Specifically, the winding temperature T B of the coiling temperature T T and the tail end of the leading end portion of the hot rolled strip and 600 ° C. or higher, the coiling temperature T C of the central portion to 530-570 ° C. Is preferred. Here, the tip of the hot-rolled steel strip is within 20% of the total length of the steel strip from the tip of the hot-rolled steel strip, and the tail end is within 30% of the total length of the steel strip from the tail of the hot-rolled steel strip, The central part shall be within 25% of the total length of the steel strip from the center in the longitudinal direction of the hot-rolled steel strip and within 25% of the total length of the steel strip in the rear (total of 50% or less).
また、巻取り温度ＴT、ＴB、ＴCを規定する部位の中間、すなわち熱延鋼帯の先端部と中央部の間、および尾端部と中央部の間の温度は、いずれもＴCからＴT、ＴBの温度範囲で漸増あるいは漸減するように熱延鋼帯の長手方向の温度分布を調整することが好ましい。 Further, the temperature between the portions defining the coiling temperatures T T , T B , and T C , that is, between the tip and the center of the hot-rolled steel strip, and between the tail and the center is T. It is preferable to adjust the temperature distribution in the longitudinal direction of the hot-rolled steel strip so that it gradually increases or decreases in the temperature range from C to T T and T B.
このように巻取り温度を設定することによって、熱延鋼帯の全長にわたって温度履歴とフェライトノーズの位置を適正に保ち、フェライト変態を生じさせることができる。 By setting the coiling temperature in this way, the temperature history and the position of the ferrite nose can be appropriately maintained over the entire length of the hot-rolled steel strip, and ferrite transformation can be caused.
熱延鋼帯の温度分布は、ランナウトテーブル上で吹付ける冷却水の噴射条件を変化させることによって調整できる。つまり、先端部と尾端部では冷却水の噴射を停止する、あるいは噴射密度を小さくして、巻取り温度が高くなるように調整する。中央部では噴射密度を大きくして、巻取り温度が低くなるように調整する。このようにして温度分布を調整した一例を図５に示す。 The temperature distribution of the hot-rolled steel strip can be adjusted by changing the injection conditions of the cooling water sprayed on the run-out table. That is, at the tip and tail ends, the cooling water injection is stopped or the injection density is reduced to adjust the winding temperature to be high. In the central part, the jet density is increased and the winding temperature is adjusted to be low. An example of adjusting the temperature distribution in this way is shown in FIG.
そして、図５に示す巻取り温度の分布を有する熱延鋼帯をコイルに巻取り、さらに10分経過した後に保熱カバーで覆い、104〜105.5秒の間コイルの内周および外周から電気加熱を行なった後に冷却した場合の、コイルの外周部の温度履歴TE（計算結果）と中央部の温度履歴MID（計算結果）を図６に示す。図６中のフェライトノーズＡ〜Ｃは図２と同じである。 Then, the hot-rolled steel strip having the winding temperature distribution shown in FIG. 5 is wound around the coil, covered with a heat insulating cover after 10 minutes, and from the inner and outer circumferences of the coil for 10 4 to 10 5.5 seconds. FIG. 6 shows the temperature history TE (calculation result) of the outer peripheral portion of the coil and the temperature history MID (calculation result) of the central portion when the coil is cooled after being electrically heated. Ferrite noses A to C in FIG. 6 are the same as those in FIG.
図６から明らかなように、コイルの外周部（すなわち熱延鋼帯の尾端部）では600℃を超える温度に102秒程度保持されているが、内部酸化の発生が懸念されるレベルではない。またコイルの外周部および中央部が、ともに550℃を超える温度に105秒程度保持されており、本発明に係る成分を有する熱延鋼帯では、全長にわたってフェライト変態が生じる。 As is clear from FIG. 6, the coil outer periphery (ie, the tail end of the hot-rolled steel strip) is maintained at a temperature exceeding 600 ° C. for about 10 2 seconds, but at a level at which internal oxidation is a concern. Absent. The outer peripheral portion and the central portion of the coil is held about 10 5 seconds to a temperature both exceeds 550 ° C., the hot rolled strip having a component according to the present invention, ferrite transformation occurs over the entire length.
このようして熱延鋼帯をコイルに巻取った後の、高強度鋼板を製造するまでの一連の工程（たとえば酸洗、冷間圧延、焼鈍等）は、何ら制約を受けることなく、通常通りの設定で操業できる。そして熱延鋼帯が軟質な金属組織を有する故に、得られた高強度鋼板においても、冷間圧延に起因する脆化が抑制され、優れた成形性を発現する。 A series of steps (for example, pickling, cold rolling, annealing, etc.) until a high-strength steel sheet is manufactured after winding the hot-rolled steel strip in a coil in this way is usually not subject to any restrictions. Can operate in street settings. And since a hot-rolled steel strip has a soft metal structure, also in the obtained high strength steel plate, the embrittlement resulting from cold rolling is suppressed and the outstanding formability is expressed.
表２に示す成分の鋼スラブ（鋼記号Ｄ〜Ｉ）を、連続熱間圧延機で圧延して、幅1200mm、板厚2.0〜3.5mmの熱延鋼帯とし、引き続き、直径760mmのマンドレルを用いてコイルに巻取った。 Steel slabs (steel symbols D to I) with the components shown in Table 2 are rolled with a continuous hot rolling mill to form a hot rolled steel strip having a width of 1200 mm and a thickness of 2.0 to 3.5 mm. And wound up on a coil.
その熱延鋼帯の先端部の巻取り温度ＴTと尾端部の巻取り温度ＴB、中央部の巻取り温度ＴC、および各部位の全長に対する割合は表３に示す通りである。なお表３にて、中央部の全長に対する割合は、熱延鋼帯の中央から前後に設けられる範囲の合計を示す。たとえばNo.６の場合、中央部の割合が70％であるが、これは熱延鋼帯の中央から前方に鋼帯全長の35％および後方に鋼帯全長の35％の範囲を意味する。 Coiling temperature T B of the coiling temperature T T and the tail end of the leading end portion of the hot rolled strip, coiling temperature T C of the central portion, and the ratio of the total length of each part is as shown in Table 3. In Table 3, the ratio with respect to the total length of the central portion indicates the total of the ranges provided before and after the center of the hot-rolled steel strip. For example, in the case of No. 6, the ratio of the central portion is 70%, which means a range of 35% of the entire length of the steel strip from the center of the hot-rolled steel strip and 35% of the total length of the steel strip behind.
保熱手段としての保熱カバー、および加熱手段としての電気加熱の使用の有無を、表３に併せて示す。なお保熱カバーを使用した場合の、巻取りを完了した後、保熱カバーで覆うまでの所要時間は８〜12分であった。 Table 3 also shows the presence / absence of use of a heat retaining cover as the heat retaining means and electric heating as the heating means. When the heat insulation cover was used, the time required for covering with the heat insulation cover after completing the winding was 8 to 12 minutes.
このようにしてコイルに巻取った熱延鋼帯を、塩酸で酸洗し、さらに５スタンドのタンデムミルで総圧下率50％の冷間圧延を行なった後、800℃で30秒保持して焼鈍を施した。そして冷間圧延にて、熱延鋼帯の尾端におけるゲージ変動の有無を調査した。その結果を表３に示す。表３中の○はゲージ変動が生じなかったもの、×はゲージ変動が発生したものである。ゲージ変動は、板厚の寸法精度の低下が原因で発生するので、ゲージ変動が生じなかったもの（○）は、寸法精度が良好であることを意味する。 The hot-rolled steel strip wound on the coil in this way is pickled with hydrochloric acid, further cold-rolled with a 5-stand tandem mill at a total reduction of 50%, and then held at 800 ° C. for 30 seconds. Annealed. And the presence or absence of the gauge fluctuation | variation in the tail end of a hot-rolled steel strip was investigated by cold rolling. The results are shown in Table 3. In Table 3, “◯” indicates that no gauge fluctuation occurred, and “×” indicates that gauge fluctuation occurred. Gauge fluctuations occur due to a decrease in the dimensional accuracy of the plate thickness, and those without gauge fluctuations (◯) mean that the dimensional accuracy is good.
また、冷間圧延の荷重の変化を調査した結果を表３に示す。表３中の○は荷重が通常の範囲で圧延できたもの、×は荷重が増加したため、所定の板厚まで圧延できなかったものである。冷間圧延の荷重が増加せず、通常の範囲で圧延できたもの（○）は、製造コスト増大、工程増加することなく、成形性に優れた高強度鋼板を製造することが可能なことを意味する。 Table 3 shows the results of investigating changes in the cold rolling load. ○ in Table 3 indicates that the load could be rolled in a normal range, and × indicates that the load could not be rolled to a predetermined plate thickness because the load increased. The cold rolling load does not increase and can be rolled in the normal range (○) indicates that it is possible to manufacture a high-strength steel sheet with excellent formability without increasing manufacturing costs and processes. means.
さらに、冷間圧延によって得られた高強度鋼板の内部酸化に起因する欠陥の有無を調査した結果を表３に示す。表３中の○は欠陥が認められなかったもの、×は欠陥が発生したものである。 Furthermore, Table 3 shows the results of investigating the presence or absence of defects due to internal oxidation of the high-strength steel sheet obtained by cold rolling. ○ in Table 3 indicates that no defect was observed, and × indicates that a defect occurred.
従来例であるNo.１は、Mn含有量が3.1質量％未満と小さいので、本発明を適用せず、熱延鋼帯の全長を同一の巻取り温度で巻取った後、保熱カバーを使用せずに空冷しても、冷間圧延の操業および高強度鋼板の寸法精度、表面性状に問題はない。 Since No. 1 which is a conventional example has a small Mn content of less than 3.1% by mass, the present invention is not applied, and after the entire length of the hot-rolled steel strip is wound at the same winding temperature, Even if it is air-cooled without being used, there is no problem in the cold rolling operation, the dimensional accuracy of the high-strength steel sheet, and the surface properties.
従来例であるNo.２、３は、巻取り温度を低く設定したので、熱延鋼帯の先端部と尾端部でゲージ変動が発生し、巻取り温度を高く設定すると、熱延鋼帯の中央部で内部酸化が発生した。 In No. 2 and 3 which are conventional examples, since the coiling temperature was set low, gauge fluctuations occurred at the tip and tail ends of the hot-rolled steel strip, and when the coiling temperature was set high, Internal oxidation occurred at the center of the area.
比較例であるNo.４、５は、保熱カバーと電気加熱を使用して熱延鋼帯（No.２、３と同じ成分）を保熱し、さらに加熱した後で冷却したが、巻取り温度が全長にわたって同一であるから、得られた高強度鋼板の寸法精度、表面性状が劣化した。 Nos. 4 and 5 which are comparative examples use a heat-retaining cover and electric heating to heat the hot-rolled steel strip (same components as Nos. 2 and 3), and after further heating and cooling, Since the temperature was the same over the entire length, the dimensional accuracy and surface properties of the obtained high-strength steel sheet deteriorated.
比較例であるNo.６、７は、熱延鋼帯（No.２、３と同じ成分）の先端部および尾端部の巻取り温度ＴTBを、中央部の巻取り温度ＴCよりも高くし、かつNo.７では保熱カバーを用いて保熱しながら冷却したが、いずれも巻取り後の冷却速度が大きいので、ゲージ変動が発生した。 Comparative examples No.6,7 is the coiling temperature T TB of tip and tail end of the hot rolled strip (same ingredients as Nanba2,3), than the coiling temperature T C of the central portion In No. 7, it was cooled while keeping heat using a heat insulating cover. However, since the cooling rate after winding was high, gauge fluctuation occurred.
発明例であるNo.８は、Mn含有量がNo.１よりも大きいものの、本発明の範囲を満たす熱延鋼帯に本発明を適用した例であり、冷間圧延の操業および高強度鋼板の寸法精度、表面性状に問題はない。 Invention Example No. 8 is an example in which the present invention is applied to a hot-rolled steel strip satisfying the scope of the present invention, although the Mn content is larger than No. 1, operation of cold rolling and high strength steel sheet There is no problem in dimensional accuracy and surface properties.
比較例であるNo.10は、Mn含有量が本発明の範囲を超える鋼Ｆで電気加熱を使用しなかった例、No.12は、Mn含有量が本発明の範囲を超える鋼Ｇで電気加熱を使用しなかった例、No.14は、成分が本発明の範囲を満たす熱延鋼帯に保熱カバーと電気加熱を使用しなかった例であり、いずれも熱延鋼帯を軟質化できず、冷延圧延の荷重が増大した。 No. 10, which is a comparative example, is an example in which electric heating is not used with steel F having an Mn content exceeding the range of the present invention, and No. 12 is an electric with steel G having an Mn content exceeding the range of the present invention. An example in which heating was not used, No. 14 was an example in which a heat-retaining cover and electric heating were not used for a hot-rolled steel strip whose components satisfy the scope of the present invention, both of which softened the hot-rolled steel strip It was not possible, and the load of cold rolling increased.
発明例であるNo.11、13は、本発明の範囲を満たす熱延鋼帯に本発明を適用した例であり、冷間圧延の操業および高強度鋼板の寸法精度、表面性状に問題はない。なお、No.９は、巻取り温度が高い部位である熱延鋼帯の先端部の割合が大きい例、No.15は、巻取り温度が高い部位である熱延鋼帯の尾端部の割合が大きい例であり、それぞれの位置で内部酸化に起因する欠陥が発生したが、その鋼帯長さは短いものであり、この部分を切り落とすことにより、残部は寸法精度、表面性状に優れた高強度鋼板を得ることができるので、許容される発明例とした。 Invention Examples No. 11 and 13 are examples in which the present invention is applied to a hot-rolled steel strip that satisfies the scope of the present invention, and there is no problem in cold rolling operation, dimensional accuracy of high-strength steel sheets, and surface properties. . In addition, No. 9 is an example in which the ratio of the tip of the hot-rolled steel strip, which is a part with a high winding temperature, is large, and No. 15 is the tail end part of the hot-rolled steel strip, which is a part with a high winding temperature. This is an example of a large proportion, and defects due to internal oxidation occurred at each position, but the steel strip length was short, and by cutting this part off, the remainder was excellent in dimensional accuracy and surface properties Since a high-strength steel plate can be obtained, it was set as the allowable invention example.
以上のように、板厚の変動（すなわちゲージ変動）に起因する寸法精度の低下、および内部酸化に起因する表面性状の劣化が発生し易いMn含有量の多い成形性に優れた高強度鋼板を製造するにあたって、本発明を適用すれば、良好な寸法精度と表面性状を有し、かつ成形性に優れた高強度鋼板を得ることができる。 As described above, a high-strength steel sheet excellent in formability with a high Mn content is likely to cause a reduction in dimensional accuracy due to fluctuations in plate thickness (that is, gauge fluctuations) and surface properties due to internal oxidation. In manufacturing, if the present invention is applied, a high-strength steel sheet having excellent dimensional accuracy and surface properties and excellent formability can be obtained.
Claims (2)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015019063A JP6202012B2 (en) | 2015-02-03 | 2015-02-03 | Manufacturing method of high-strength steel sheet with excellent formability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015019063A JP6202012B2 (en) | 2015-02-03 | 2015-02-03 | Manufacturing method of high-strength steel sheet with excellent formability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2016141848A true JP2016141848A (en) | 2016-08-08 |
| JP6202012B2 JP6202012B2 (en) | 2017-09-27 |
Family
ID=56569827
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2015019063A Active JP6202012B2 (en) | 2015-02-03 | 2015-02-03 | Manufacturing method of high-strength steel sheet with excellent formability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP6202012B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2020534439A (en) * | 2017-09-20 | 2020-11-26 | 宝鋼湛江鋼鉄有限公司Ｂａｏｓｔｅｅｌ Ｚｈａｎｊｉａｎｇ Ｉｒｏｎ ＆ Ｓｔｅｅｌ Ｃｏ．， Ｌｔｄ． | In-line production method for improving the precipitation strengthening effect of Ti microalloyed hot-rolled high-strength steel |
| JP2020534438A (en) * | 2017-09-20 | 2020-11-26 | 宝鋼湛江鋼鉄有限公司Ｂａｏｓｔｅｅｌ Ｚｈａｎｊｉａｎｇ Ｉｒｏｎ ＆ Ｓｔｅｅｌ Ｃｏ．， Ｌｔｄ． | How to soften high-strength Q & P steel hot-rolled coil |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5166219A (en) * | 1974-12-05 | 1976-06-08 | Nippon Kokan Kk | |
| JPS55154529A (en) * | 1979-05-18 | 1980-12-02 | Nippon Steel Corp | Manufacture of soft steel sheet by continuous annealing |
| JPS60248822A (en) * | 1984-05-22 | 1985-12-09 | Nippon Steel Corp | Manufacture of cold rolled steel sheet with superior workability |
| US6679957B1 (en) * | 1998-09-15 | 2004-01-20 | Acciai Speciali S.P.A. | Process for thermal treatment of steel strip |
| JP2015175004A (en) * | 2014-03-13 | 2015-10-05 | Ｊｆｅスチール株式会社 | Production method of high strength steel sheet excellent in formability |
-
2015
- 2015-02-03 JP JP2015019063A patent/JP6202012B2/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5166219A (en) * | 1974-12-05 | 1976-06-08 | Nippon Kokan Kk | |
| JPS55154529A (en) * | 1979-05-18 | 1980-12-02 | Nippon Steel Corp | Manufacture of soft steel sheet by continuous annealing |
| JPS60248822A (en) * | 1984-05-22 | 1985-12-09 | Nippon Steel Corp | Manufacture of cold rolled steel sheet with superior workability |
| US6679957B1 (en) * | 1998-09-15 | 2004-01-20 | Acciai Speciali S.P.A. | Process for thermal treatment of steel strip |
| JP2015175004A (en) * | 2014-03-13 | 2015-10-05 | Ｊｆｅスチール株式会社 | Production method of high strength steel sheet excellent in formability |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2020534439A (en) * | 2017-09-20 | 2020-11-26 | 宝鋼湛江鋼鉄有限公司Ｂａｏｓｔｅｅｌ Ｚｈａｎｊｉａｎｇ Ｉｒｏｎ ＆ Ｓｔｅｅｌ Ｃｏ．， Ｌｔｄ． | In-line production method for improving the precipitation strengthening effect of Ti microalloyed hot-rolled high-strength steel |
| JP2020534438A (en) * | 2017-09-20 | 2020-11-26 | 宝鋼湛江鋼鉄有限公司Ｂａｏｓｔｅｅｌ Ｚｈａｎｊｉａｎｇ Ｉｒｏｎ ＆ Ｓｔｅｅｌ Ｃｏ．， Ｌｔｄ． | How to soften high-strength Q & P steel hot-rolled coil |
| US11384406B2 (en) | 2017-09-20 | 2022-07-12 | Baosteel Zhanjian Iron & Steel Co., Ltd. | Production method for inline increase in precipitation toughening effect of Ti microalloyed hot-rolled high-strength steel |
| JP7320513B2 (en) | 2017-09-20 | 2023-08-03 | 宝鋼湛江鋼鉄有限公司 | Inline Production Method for Improving Precipitation Strengthening Effect of Ti Micro-alloyed Hot-rolled High-strength Steel |
| JP7320512B2 (en) | 2017-09-20 | 2023-08-03 | 宝鋼湛江鋼鉄有限公司 | Method for softening high-strength Q&P steel hot-rolled coil |
| US11981972B2 (en) | 2017-09-20 | 2024-05-14 | Baosteel Zhanjian Iron & Steel Co., Ltd. | Softening method for high-strength Q and P steel hot roll |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6202012B2 (en) | 2017-09-27 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP2589678B1 (en) | High-strength steel sheet with excellent processability and process for producing same | |
| JP4640130B2 (en) | High-strength cold-rolled steel sheet with small variation in mechanical properties and method for producing the same | |
| JP6171994B2 (en) | Manufacturing method of high-strength steel sheet with excellent formability | |
| JP5487203B2 (en) | High-strength steel sheet and galvanized steel sheet for high processing with excellent surface characteristics and method for producing the same | |
| JP4650006B2 (en) | High carbon hot-rolled steel sheet excellent in ductility and stretch flangeability and method for producing the same | |
| JP2017048412A (en) | Hot-dip galvanized steel sheet, alloyed hot-dip galvanized steel sheet and production methods therefor | |
| JP2005126733A (en) | Steel sheet for hot press having excellent hot workability, and automotive member | |
| JP5316634B2 (en) | High-strength steel sheet with excellent workability and method for producing the same | |
| JP5967318B1 (en) | High-strength hot-dip galvanized steel sheet and manufacturing method thereof | |
| JP6079726B2 (en) | Manufacturing method of high-strength steel sheet | |
| JP2023093564A (en) | Hot-forming member | |
| JP2010502845A (en) | High strength galvanized steel sheet with excellent mechanical properties and surface quality and method for producing the same | |
| JP2016511795A (en) | Cold rolled flat steel product for applying deep drawing and method for producing the same | |
| JP6222040B2 (en) | High formability and high strength cold-rolled steel sheet excellent in chemical conversion treatment and production method thereof | |
| WO2013102982A1 (en) | High carbon hot-rolled steel sheet with excellent hardenability and minimal in-plane anisotropy, and method for producing same | |
| JP5407552B2 (en) | Hot-rolled steel sheet with excellent formability and manufacturing method thereof | |
| JP6252499B2 (en) | Manufacturing method of hot-rolled steel strip, cold-rolled steel strip and hot-rolled steel strip | |
| JP6202012B2 (en) | Manufacturing method of high-strength steel sheet with excellent formability | |
| JP2013185240A (en) | High-tension cold-rolled steel sheet, high-tension plated steel sheet, and method for producing them | |
| JP4192857B2 (en) | High-strength cold-rolled steel sheet and manufacturing method thereof | |
| JP4367205B2 (en) | Strain aging treatment method for steel sheet and method for producing high-strength structural member | |
| JP2009030148A (en) | Method for manufacturing cold-rolled steel sheet and plated steel sheet | |
| JP3417589B2 (en) | Method for producing high-strength hot-rolled steel sheet with excellent stretch formability at high yield | |
| JP3417588B2 (en) | Method for producing thin high-strength hot-rolled steel sheets with excellent stretch formability at high yield | |
| JP3925063B2 (en) | Cold-rolled steel sheet excellent in press formability and strain age hardening characteristics and method for producing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20160926 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20170721 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20170801 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20170814 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 6202012 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |