JP2005281816A - High strength cold rolled steel sheet having satisfactory formability and excellent projection weldability, and production method therefor - Google Patents
High strength cold rolled steel sheet having satisfactory formability and excellent projection weldability, and production method therefor Download PDFInfo
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本発明は高強度冷延鋼板及びその製造方法に係り、特に自動車のフロントサイドメンバーなど形状が複雑でかつ、プロジェクション溶接がされる部材の製造に用いる、成形性が良好でかつ、プロジェクション溶接性が優れた高強度冷延鋼板及びその製造方法に関する。 The present invention relates to a high-strength cold-rolled steel sheet and a method for producing the same, and in particular, the shape of the front side member of an automobile is complex, and the formability is good and the projection weldability is good for use in producing a member to be projection welded. The present invention relates to an excellent high-strength cold-rolled steel sheet and a method for producing the same.
自動車の車体構成材や外装材などに用いる鋼材は、車体重量の軽減のため高強度であることが要求され、そのため各種の高強度鋼板が提供されている。なかでも自動車のフロントサイドメンバーなど複雑な形状をもちかつ、他の部材と結合させるためにナットなどを溶接する部材は引張り強さ(TS)が780MPa以上という高強度と伸び(El)が20%以上(好ましくは22%以上)さらに降伏比(YR)が65%以下という成形性が要求されるとともにプロジェクションがよいことが要求される。 Steel materials used for automobile body components and exterior materials are required to have high strength in order to reduce the weight of the vehicle body. For this reason, various high-strength steel plates are provided. Among them, members that have complicated shapes such as the front side members of automobiles and weld nuts to join other members have a high tensile strength (TS) of over 780 MPa and an elongation (El) of 20%. Above (preferably 22% or more), the yield ratio (YR) is required to be 65% or less, and the projection is required to be good.
このような自動車用鋼材の要求のうち、高強度で成形性が良好であることを満たすために、たとえば特許文献1には、C, Mn, Nb, Ti,さらにCr, B等の含有成分量を適正化することによって第2相組織を有する複合組織とし、さらに再結晶焼鈍後に500℃前後の温度域に滞留させる間に溶融亜鉛めっきを施しその後の冷却速度を規制することによって、生成した第2相の必要以上の硬化を防止し、低降伏比高強度高強度溶融亜鉛めっき鋼板を得るという手段が開示されている。 In order to satisfy the high strength and good formability among the requirements for such steel materials for automobiles, for example, Patent Document 1 discloses the amount of components such as C, Mn, Nb, Ti, and Cr, B. A composite structure having a second phase structure is obtained by optimizing the temperature, and further, a hot dip galvanizing is performed while retaining in a temperature range of about 500 ° C. after recrystallization annealing, and the subsequent cooling rate is regulated. Means have been disclosed that prevent the two phases from being hardened more than necessary and obtain a low yield ratio high strength high strength hot dip galvanized steel sheet.
しかしながら、上記特許文献1に開示されている手段は、それにより高強度で成形性が良好な亜鉛めっき鋼板を提供することはできるが、プロジェクション溶接についての配慮を欠くものである。プロジェクション溶接、特に、突合せプロジェクション溶接はアプセット溶接と類似の溶接過程を経るものであって接合面に酸化物などが残留しないことが要請され、そのため鋼板の機械的性質とは異なる特別な配慮がなされなければならない。 However, the means disclosed in Patent Document 1 can provide a galvanized steel sheet having high strength and good formability, but lacks consideration for projection welding. Projection welding, especially butt projection welding, is a process similar to upset welding and requires that no oxides remain on the joint surface. Therefore, special considerations differing from the mechanical properties of steel sheets are made. There must be.
本発明は、このような従来技術では達成されなかった引張り強さ(TS)が780MPa以上、伸び(El)が20%以上、降伏比(YR)が65%以下であるという鋼板の機械的性質とプロジェクション溶接性の両立を図り、成形性が良好でかつ、プロジェクション溶接性が優れた高強度冷延鋼板及びその製造方法を提案することを目的とする。 In the present invention, the mechanical properties of a steel sheet that have a tensile strength (TS) of 780 MPa or more, an elongation (El) of 20% or more, and a yield ratio (YR) of 65% or less, which could not be achieved by such conventional techniques. An object of the present invention is to propose a high-strength cold-rolled steel sheet having excellent formability and projection weldability, and a method for producing the same.
本発明に係る高強度冷延鋼板は、質量比で、C:0.075〜0.105%、Si:0.50〜0.65%、Mn:2.45〜2.65%を含有し、P:0.020%以下、S:0.005%以下、Al:0.05%以下に制限され、残部不可避的不純物を除き実質的にFeからなり、引張り強さ(TS)が780MPa以上、伸び(El)が20%以上、降伏比(YR)が65%以下と高強度で成形性が良好でかつ、プロジェクション溶接性が優れている。この高強度冷延鋼板は、さらにB:0.00015〜0.0020%を含有することによりプロジェクション溶接性を害することなく、その機械的性質の一層の向上を図ることができる。 The high-strength cold-rolled steel sheet according to the present invention contains, by mass ratio, C: 0.075 to 0.105%, Si: 0.50 to 0.65%, Mn: 2.45 to 2.65%, P: 0.020% or less, S: 0.005% or less. , Al: Limited to 0.05% or less, substantially composed of Fe except for the inevitable impurities of the balance, tensile strength (TS) is 780MPa or more, elongation (El) is 20% or more, yield ratio (YR) is 65% It has the following high strength, good formability, and excellent projection weldability. This high-strength cold-rolled steel sheet can further improve its mechanical properties without impairing the projection weldability by further containing B: 0.00015 to 0.0020%.
上記プロジェクション溶接性が優れた高強度冷延鋼板は、質量比で、C:0.075〜0.105%、Si:0.50〜0.65%、Mn:2.45〜2.65%を含有し、P:0.020%以下、S:0.005%以下、Al:0.05%以下に制限され、残部不可避的不純物を除き実質的にFeからなる鋼素材を熱延した後、冷延し、得られた冷延板に対し775〜830℃に加熱した後300℃以下まで15℃/s以上の速度で急速冷却行なう熱処理を施すことによって製造することができる。この場合、鋼素材にはさらにB:0.00015〜0.0020%を含有させることができる。 The high-strength cold-rolled steel sheet having excellent projection weldability contains, by mass ratio, C: 0.075 to 0.105%, Si: 0.50 to 0.65%, Mn: 2.45 to 2.65%, P: 0.020% or less, and S: It is limited to 0.005% or less, Al: 0.05% or less, and the steel material consisting essentially of Fe, excluding the remaining inevitable impurities, is hot-rolled and then cold-rolled, and the resulting cold-rolled sheet is heated to 775-830 ° C. After heating, it can be produced by applying a heat treatment for rapid cooling to 300 ° C. or lower at a rate of 15 ° C./s or higher. In this case, the steel material can further contain B: 0.00015 to 0.0020%.
本発明により、成形性が良好でかつ、プロジェクション溶接性が優れた高強度冷延鋼板の供給が可能になる。それにより、自動車のフロントサイドメンバーなど形状が複雑な部材への成形とプロジェクション溶接による接合が容易かつ確実に行なえるようになり、自動車の軽量化に寄与する。 According to the present invention, it is possible to supply a high-strength cold-rolled steel sheet having good formability and excellent projection weldability. As a result, it becomes possible to easily and reliably form a member having a complicated shape, such as a front side member of an automobile, and join by projection welding, thereby contributing to weight reduction of the automobile.
本発明に係る高強度冷延鋼板は、質量比で、C:0.075〜0.105%、Si:0.50〜0.65%、Mn:2.45〜2.65%を含有し、P:0.020%以下、S:0.005%以下、Al:0.05%以下に制限され、残部不可避的不純物を除き実質的にFeからなる組成を有する。以下、これら成分の限定理由について説明する。 The high-strength cold-rolled steel sheet according to the present invention contains, by mass ratio, C: 0.075 to 0.105%, Si: 0.50 to 0.65%, Mn: 2.45 to 2.65%, P: 0.020% or less, S: 0.005% or less. Al: It is limited to 0.05% or less, and has a composition substantially composed of Fe except for the remaining inevitable impurities. Hereinafter, the reasons for limiting these components will be described.
Cは鋼板に所定の強度を付与し、また本発明に係る鋼を製造する際に採用される熱処理によって複合組織型高強度鋼板とし、高強度を達成するとともに成形性を良好とするために必要な元素である。しかし、その含有量が少な過ぎるときには、鋼板に十分な強度、たとえば780MPa以上を付与することができず、一方その含有量が高すぎるときには、強度が高すぎて加工性を害するばかりか、製造時スラブ割れなどを生じる原因となる。したがって、Cの含有量は0.075〜0.105%(質量比、以下同様)、好ましくは0.080〜0.100%とする。 C is required to give a predetermined strength to the steel sheet and to make a composite structure type high-strength steel sheet by heat treatment adopted when manufacturing the steel according to the present invention, to achieve high strength and good formability. Element. However, when the content is too small, sufficient strength, for example, 780 MPa or more cannot be imparted to the steel sheet. On the other hand, when the content is too high, the strength is too high and the workability is impaired. It causes slab cracking. Therefore, the C content is 0.075 to 0.105% (mass ratio, the same applies hereinafter), preferably 0.080 to 0.100%.
Siは複合組織型高強度鋼板においてフェライト相分率を上昇させ、それにより伸び(El)を向上させる元素である。また、プロジェクション溶接にあたり、溶接面に生成する酸化物をシリケート系とすることによって溶接面から排出しやすくして、プロジェクション溶接性を向上させる元素である。この効果を得るために、本発明ではSiを0.50%以上含有させる。しかしながら、Siは鋼板表面に濃化し、それにより塗装性、めっき性を低下させる。この影響は特にいわゆる無酸洗材に現れやすく、Si含有量が0.65%を超えると、Siの表面濃化により鋼板表面のSi濃度が非常に高くなって塗装後耐食性が著しく劣化する。したがって、本発明ではSiの含有量は0.50〜0.65%とする。 Si is an element that increases the ferrite phase fraction and thereby improves the elongation (El) in a high-strength steel sheet having a composite structure. Further, in projection welding, it is an element that improves the projection weldability by making it easy to discharge from the welding surface by making the oxide generated on the welding surface into a silicate system. In order to obtain this effect, 0.50% or more of Si is contained in the present invention. However, Si concentrates on the surface of the steel sheet, thereby reducing paintability and plating properties. This effect is particularly likely to occur in so-called non-pickling materials. When the Si content exceeds 0.65%, the Si concentration on the surface of the steel sheet becomes very high due to the surface concentration of Si, and the corrosion resistance after coating is remarkably deteriorated. Therefore, in the present invention, the Si content is set to 0.50 to 0.65%.
Mnはいわゆるオーステナイト生成促進元素であり、Cと同様、鋼板に所定の強度を付与し、また本発明に係る鋼を製造する際に採用される熱処理によって複合組織型高強度鋼板とし、高強度を達成するとともに成形性を良好にするために必要な元素である。しかし、その含有量が2.45%より少ないときには、鋼板に十分な強度、たとえば引張り強さ780MPa以上を付与することができず、一方その含有量が2.65%より高いと、適正な複合型組織とすることができず、強度が高すぎて加工性を害する原因となる。したがって、Mnの含有量は2.45〜2.65%とする。 Mn is a so-called austenite formation promoting element. Like C, Mn gives a predetermined strength to the steel sheet, and a high-strength steel sheet having a composite structure type by heat treatment adopted when manufacturing the steel according to the present invention. It is an element necessary to achieve and improve moldability. However, when the content is less than 2.45%, sufficient strength, for example, a tensile strength of 780 MPa or more cannot be imparted to the steel sheet, while when the content is higher than 2.65%, an appropriate composite structure is obtained. It cannot be performed, and the strength is too high, which causes the workability to be damaged. Therefore, the Mn content is 2.45 to 2.65%.
Pは0.020%を超えて存在するとプロジェクション溶接性を害し、またスラブの中心に偏析することによってフェライトバンドが形成される原因となり、圧延方向に直角方向の曲げ加工性を劣化させる。また、Sは0.005%を超えて存在するとプロジェクション溶接性を害し、また加工性を害する。このような理由により、P及びSはそれぞれ0.020%以下、0.005%以下に制限される。 If P exceeds 0.020%, projection weldability is impaired, and segregation at the center of the slab causes a ferrite band to be formed, which deteriorates bending workability in a direction perpendicular to the rolling direction. Further, if S exceeds 0.005%, it impairs the projection weldability and also the workability. For these reasons, P and S are limited to 0.020% or less and 0.005% or less, respectively.
Alは製鋼の際、脱酸剤として鋼中に添加される。また、結晶粒を微細化させる効果もある。しかし、0.05%を超えて残留してもその効果が飽和するだけであるので0.05%以下に制限する。 Al is added to the steel as a deoxidizer during steelmaking. In addition, there is an effect of making the crystal grains finer. However, even if it exceeds 0.05%, the effect is only saturated, so it is limited to 0.05% or less.
その他の成分は、不可避的不純物を除きFeである。不可避的不純物としてはO、Nその他のトランプエレメントが挙げられる。これらの含有量は極力低値に抑制するのが望ましい。 Other components are Fe except for inevitable impurities. Inevitable impurities include O, N and other trump elements. It is desirable to suppress these contents as low as possible.
なお、Bは固溶状態でオーステナイト粒界に偏析してオーステナイトを比較的低温まで安定に存在させることにより、複合組織における硬質相の生成を促進する元素である。本発明においては、Bを0.00015〜0.00200(1.5〜20ppm)の範囲で含有させることができ、それによって適正な複合型組織を得ることができるようになる。なお、Bは不可避不純物として1ppm以下含有される場合があるが、本発明はこのような場合を排除しない。 B is an element that promotes the formation of a hard phase in the composite structure by segregating in the austenite grain boundary in a solid solution state and allowing austenite to exist stably to a relatively low temperature. In the present invention, B can be contained in the range of 0.00015 to 0.00200 (1.5 to 20 ppm), whereby an appropriate composite structure can be obtained. B may be contained in an amount of 1 ppm or less as an inevitable impurity, but the present invention does not exclude such a case.
本発明に係る高強度冷延銅板は、引張り強さ(TS)780MPa以上という高強度と、伸び(El)20%以上(より好ましくは22%以上)、降伏比(YR)65%以下という良好な成形性を有する。このような高強度と成形性を両立させた本発明に係る高強度冷延鋼板の組織は、フェライト相を含むともにフェライト相以外の第2相(硬質相ともいう)にマルテンサイト相を含む複合組織となっている。このような複合組織とすることにより、高強度でかつ良好な成形性を有することができる。なお、上記硬質相は、概ねマルテンサイト相およびベイナイト相からなる。 The high-strength cold-rolled copper sheet according to the present invention has a high tensile strength (TS) of 780 MPa or higher, an elongation (El) of 20% or more (more preferably 22% or more), and a yield ratio (YR) of 65% or less. Have excellent moldability. The structure of the high-strength cold-rolled steel sheet according to the present invention that achieves both high strength and formability is a composite containing a martensite phase in the second phase (also referred to as a hard phase) other than the ferrite phase. It is an organization. By setting it as such a composite structure, it can have high intensity | strength and favorable moldability. The hard phase generally consists of a martensite phase and a bainite phase.
上記の組成、組織を有することにより本発明にかかる鋼は、概ね引張り強さ(TS)780〜860MPa、耐力(降伏点)(YP)460〜550MPa、伸び(El)20〜24%の機械的性質を有し、かつプロジェクション溶接性に優れる。 By having the above composition and structure, the steel according to the present invention has a tensile strength (TS) of 780 to 860 MPa, a proof stress (yield point) (YP) of 460 to 550 MPa, and an elongation (El) of 20 to 24%. It has properties and is excellent in projection weldability.
かかる特性を有する鋼は、質量比で、C:0.075〜0.105%、Si:0.50〜0.65%、Mn:2.45〜2.65%を含有し、P:0.020%以下、S:0.005%以下、Al:0.05%以下に制限され、残部不可避的不純物を除き実質的にFeからなる組成、又はこれに加えてB:0.00015〜0.0020%を含有する組成のスラブを出発素材とし、これを常法により加熱、熱延してたとえば厚さ2.6mm程度の熱延板を得、得られた熱延板に対して常法に従い酸洗、冷延を行なってたとえば最終板厚1.8mm程度の冷延板とし、これに以下の熱処理を施すことによって製造することができる。なお、熱処理は連続ラインによって行なうことが好ましい。 Steel having such characteristics contains, by mass ratio, C: 0.075 to 0.105%, Si: 0.50 to 0.65%, Mn: 2.45 to 2.65%, P: 0.020% or less, S: 0.005% or less, Al: 0.05 %, And a composition consisting essentially of Fe except the inevitable impurities of the remainder, or in addition to this, a slab having a composition containing B: 0.00015 to 0.0020%, which is heated and heated by a conventional method. To obtain a hot-rolled sheet having a thickness of, for example, about 2.6 mm, and pickling and cold-rolling the obtained hot-rolled sheet according to a conventional method to obtain a cold-rolled sheet having a final thickness of, for example, about 1.8 mm. Can be manufactured by performing the following heat treatment. The heat treatment is preferably performed by a continuous line.
加熱温度:775〜830℃
冷延板の加熱温度は、製品の組織をフェライト相と硬質相を有する複合組織として高強度とするとともに成形性付与するためにフェライト−オーステナイト2相領域で行なわれる。加熱温度が775℃未満であるときには、硬質相を十分に生成するに足る量のオーステナイトが生成せず、製品強度が不足することになる。一方、加熱温度が830℃超であるときには、フェライト相の量が少なくなりすぎ、製品の延性が不足する結果を招く。
Heating temperature: 775 ~ 830 ℃
The heating temperature of the cold-rolled sheet is performed in a ferrite-austenite two-phase region in order to increase the strength of the product structure as a composite structure having a ferrite phase and a hard phase and to provide formability. When the heating temperature is less than 775 ° C., an amount of austenite sufficient to generate a hard phase is not generated, resulting in insufficient product strength. On the other hand, when the heating temperature is higher than 830 ° C., the amount of ferrite phase becomes too small, resulting in insufficient product ductility.
冷却条件:15℃/s以上
上記フェライト−オーステナイト2相領域からの冷却速度は、オーステナイトを硬質相に変態させ、それによって複合型組織を得て高強度とするとともに良好な成形性を得るための条件として定められる。冷却速度が15℃/s未満の場合には、オーステナイト相がパーライト変態し、あるいは上部ベイナイト相を生じて所望の強度、延性を有する製品を得ることができない。材質上の観点からは、冷却速度の上限は設ける必要はないが、30℃/sを超えると鋼板の冷却が均一に行なわれず、鋼板の平坦度を害する。したがって冷却条件は15℃/s以上の急速冷却、好ましくは15〜30℃/sとすべきである。なお、上記急速冷却は、上記加熱後直ちに開始してもよいが、加熱後10〜20℃程度の区間を徐冷し、しかる後上記速度で冷却することもできる。
Cooling condition: 15 ° C./s or more The cooling rate from the ferrite-austenite two-phase region is to transform austenite into a hard phase, thereby obtaining a composite structure to obtain high strength and good moldability. As a condition. When the cooling rate is less than 15 ° C./s, the austenite phase undergoes pearlite transformation or the upper bainite phase is formed, and a product having desired strength and ductility cannot be obtained. From the viewpoint of the material, it is not necessary to set an upper limit of the cooling rate, but if it exceeds 30 ° C./s, the steel sheet is not uniformly cooled, and the flatness of the steel sheet is impaired. Accordingly, the cooling condition should be rapid cooling of 15 ° C./s or more, preferably 15 to 30 ° C./s. In addition, although the said rapid cooling may be started immediately after the said heating, the area | region of about 10-20 degreeC after a heating can be gradually cooled, and it can also cool at the said speed | rate after an appropriate time.
冷却停止温度:300℃以上
冷却停止温度は上記冷却によって適当な硬度を有する硬質相が生じ、高強度としても良好な成形性が得られる温度として定められ、前記加熱温度との関係が考慮される。図1は冷延板(C:0.09%、Si:0.60%、Mn:2.5%、P:0.012%、S:0.0032%、Al:0.038%、残部Feおよび不可避的不純物)の加熱温度と冷却停止温度が製品の鋼帯の圧延方向に対し直角方向(C方向)の機械的性質に及ぼす影響を示す関係図である。ここに示すように、冷却停止温度が300℃超のときは、鋼板の強度(TS)が780MPa未満となるか、あるいは延性(El)が20%未満となる。さらに、冷却停止温度が300℃以下であっても、加熱温度が775℃未満のときあるいは830℃超のときは鋼板の強度が不十分となるか、あるいは延性不足となる。なお、図1において、強度、延性ともに満足した場合は、降伏比(YR)も65%以下を満足していることを別途確認している。
Cooling stop temperature: 300 ° C or more The cooling stop temperature is determined as a temperature at which a hard phase having an appropriate hardness is generated by the above cooling, and good moldability can be obtained even at high strength, and the relationship with the heating temperature is taken into consideration . Fig. 1 shows the heating temperature and cooling stop for cold-rolled sheets (C: 0.09%, Si: 0.60%, Mn: 2.5%, P: 0.012%, S: 0.0032%, Al: 0.038%, remaining Fe and inevitable impurities) It is a related figure which shows the influence which temperature has on the mechanical property of a perpendicular direction (C direction) with respect to the rolling direction of the steel strip of a product. As shown here, when the cooling stop temperature is higher than 300 ° C., the strength (TS) of the steel sheet is less than 780 MPa, or the ductility (El) is less than 20%. Furthermore, even when the cooling stop temperature is 300 ° C. or lower, when the heating temperature is lower than 775 ° C. or higher than 830 ° C., the strength of the steel sheet becomes insufficient or the ductility becomes insufficient. In FIG. 1, when both the strength and ductility are satisfied, it is separately confirmed that the yield ratio (YR) also satisfies 65% or less.
なお、上記冷却停止温度は、300℃以下であればそれ以外に特に限定する必要がなく、上記熱処理を連続焼鈍ラインで行なう場合、急冷停止温度の下限は、概ね240℃程度となる。また、上記急速冷却の後の冷却については、特に限定する必要はなく、設備の仕様、能力などに合わせて冷却すればよい。たとえば150℃までの区間について冷却速度が2〜4℃/sのいわゆる加速冷却を行ない、その後コイルに巻き取って自然放冷してもよい。これにより、硬質相が軟化しないようにするとともに、冷却効率を向上することができる。その際、上記冷却停止温度近傍に20〜60s保持し、しかる後加速冷却及び自然放冷することもできる。 The cooling stop temperature is not particularly limited as long as it is 300 ° C. or lower. When the heat treatment is performed in a continuous annealing line, the lower limit of the rapid cooling stop temperature is approximately 240 ° C. Further, the cooling after the rapid cooling is not particularly limited, and may be performed according to the specifications and capacity of the equipment. For example, a so-called accelerated cooling with a cooling rate of 2 to 4 ° C./s may be performed in a section up to 150 ° C., and then wound around a coil and allowed to cool naturally. Thereby, while preventing a hard phase from softening, cooling efficiency can be improved. In that case, it can hold | maintain for 20 to 60 s in the vicinity of the said cooling stop temperature, and can also carry out accelerated cooling and natural cooling after that.
表1に示す各種組成を有する厚さ1.6mmの冷延板を製造し、これに表2に示す条件の熱処理を施した。得られた製品の機械的性質、成形性及びプロジェクション溶接性は表2に併せて示す。得られた製品の機械的性質は、圧延方向に対し直角方向(C方向)から採取した試験片をJIS 5号試験片に加工し、JIS Z 2241に従い、引張り強さ(TS)、破断伸び(El)、降伏強度(YS)を測定した。また得られた引張り強さ(TS)と降伏強度(YS)から降伏比(YR=(YS/TS)×lOO(%))を算出した。ここで、伸び(El)が20%以上かつ降伏比(YR)が65%以下の場合、加工性良(△)とし、さらに伸び(El)が22%以上の場合、加工性優(○)として評価した。また、得られた製品のプロジェクション溶接性は、JIS C 9307に準拠した溶接機を用い、六角ナットをプロジェクション溶接した後、該六角ナットを剥離し、剥離強度を測定した。従来材(鋼板No.3)における剥離強度を100としたとき125以上の剥離強度を有する場合を○、125未満を×として評価した。 Cold-rolled sheets having a thickness of 1.6 mm having various compositions shown in Table 1 were manufactured, and subjected to heat treatment under the conditions shown in Table 2. Table 2 shows the mechanical properties, formability, and projection weldability of the obtained product. The mechanical properties of the obtained product are as follows. Test specimens taken from the direction perpendicular to the rolling direction (C direction) are processed into JIS No. 5 test specimens, and tensile strength (TS) and elongation at break (in accordance with JIS Z 2241) El) and yield strength (YS) were measured. The yield ratio (YR = (YS / TS) × lOO (%)) was calculated from the obtained tensile strength (TS) and yield strength (YS). Here, when the elongation (El) is 20% or more and the yield ratio (YR) is 65% or less, the workability is good (△), and when the elongation (El) is 22% or more, the workability is excellent (○). As evaluated. Further, the projection weldability of the obtained product was measured by peeling the hexagon nut after projecting the hexagon nut using a welding machine based on JIS C 9307, and measuring the peel strength. When the peel strength in the conventional material (steel plate No. 3) was 100, the case of having a peel strength of 125 or more was evaluated as ○, and the case of less than 125 was evaluated as ×.
なお、製品の組織を光学顕微鏡で観察したが、本発明鋼板では、フェライト相を有するとともにマルテンサイト相を有する複合組織となっていることを確認した。また、本発明鋼板について、穴拡げ性を調査したが、穴拡げ性率λ≧25%であり、伸びフランジ性にも問題がないことを確認した。さらに、実部品として、サイドフレームに成形し、六角ナットをプロジェクション溶接する試験を行ったが、成形時の亀裂発生などの問題はなく、また、プロジェクション溶接性も従来材に比べて格段に優れることを確認した。 In addition, although the structure | tissue of the product was observed with the optical microscope, it confirmed that it was a composite structure which has a martensite phase while having a ferrite phase in this invention steel plate. Moreover, although the hole expansibility was investigated about this invention steel plate, it was confirmed that it is a hole expansibility ratio (lambda)> = 25% and there is no problem also in stretch flangeability. Furthermore, as a real part, it was molded into a side frame and a hexagon nut was tested for projection welding. However, there were no problems such as cracking during molding, and the projection weldability was much better than conventional materials. It was confirmed.
Claims (4)
The method for producing a high-strength cold-rolled steel sheet having good formability and excellent projection weldability according to claim 3, wherein the steel material further contains B: 0.00015 to 0.0020%.
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Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
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JP2010106343A (en) * | 2008-10-31 | 2010-05-13 | Kobe Steel Ltd | Steel sheet for automotive member having excellent nut projection weldability and member |
JP2011006764A (en) * | 2009-06-29 | 2011-01-13 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet for projection welding |
JP2011006766A (en) * | 2009-06-29 | 2011-01-13 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet for resistance welding, and method for producing the same |
JP2012126943A (en) * | 2010-12-14 | 2012-07-05 | Sumitomo Metal Ind Ltd | Cold-rolled steel sheet for resistance welding, and method for producing the same |
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2004
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Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010106343A (en) * | 2008-10-31 | 2010-05-13 | Kobe Steel Ltd | Steel sheet for automotive member having excellent nut projection weldability and member |
JP2011006764A (en) * | 2009-06-29 | 2011-01-13 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet for projection welding |
JP2011006766A (en) * | 2009-06-29 | 2011-01-13 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet for resistance welding, and method for producing the same |
JP2012126943A (en) * | 2010-12-14 | 2012-07-05 | Sumitomo Metal Ind Ltd | Cold-rolled steel sheet for resistance welding, and method for producing the same |
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