WO2017086745A1 - Tôle d'acier haute résistance laminée à froid ayant une excellente aptitude au traitement sous cisaillement, et son procédé de fabrication - Google Patents

Tôle d'acier haute résistance laminée à froid ayant une excellente aptitude au traitement sous cisaillement, et son procédé de fabrication Download PDF

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WO2017086745A1
WO2017086745A1 PCT/KR2016/013362 KR2016013362W WO2017086745A1 WO 2017086745 A1 WO2017086745 A1 WO 2017086745A1 KR 2016013362 W KR2016013362 W KR 2016013362W WO 2017086745 A1 WO2017086745 A1 WO 2017086745A1
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steel sheet
rolled steel
cold rolled
high strength
relation
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Korean (ko)
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김성일
서석종
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Posco Holdings Inc
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Posco Co Ltd
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Priority to JP2018525787A priority Critical patent/JP6684905B2/ja
Priority to US15/772,644 priority patent/US20190136339A1/en
Priority to CN201680067955.6A priority patent/CN108350550B/zh
Publication of WO2017086745A1 publication Critical patent/WO2017086745A1/fr
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Definitions

  • the present invention relates to a high strength cold rolled steel sheet excellent in shear workability and a method of manufacturing the same.
  • the crack generation by the shearing process is not only small, but the crack propagation due to the frictional heat must be suppressed, and high strength and high hardness are required.
  • Patent Document 1 As the conventional high strength cold rolled steel sheet for friction plates or hardness guarantee, as described in Patent Document 1, a technique for performing annealing heat treatment after cold rolling using a recovery annealing method for a medium containing carbon steel or various alloying elements. In addition, a method using a spheroidizing heat treatment process is commonly used for high carbon steel, and Patent Document 2 proposes a technique using two cold rolling methods of cold rolling, annealing, and cold rolling.
  • a high strength steel sheet using the recovery annealing method has a problem that it is difficult to manufacture a steel having a high strength, the technique of spheroidizing heat treatment using high carbon steel and the two cold rolling technology has a problem that the manufacturing cost is high.
  • alloy components such as C, Si, Mn, Mo, Cr, which are mainly used to manufacture cold rolled high strength steel sheet, are effective to improve the strength of the steel sheet by solid solution strengthening effect. It causes unevenness of stone and microstructure. In particular, the hardenability of the steel is increased during cooling, which significantly delays the ferrite phase transformation, generates low-temperature phases (martensite and austenite phases), uneven grain boundaries, and increases cracking during shearing. It propagates easily and causes defects.
  • Patent Document 1 Application No. KR 1998-0059809
  • Patent Document 2 Application No. DE 2005-10031462
  • An object of the present invention is to provide a high strength cold rolled steel sheet having excellent shearing property capable of suppressing cracking caused by shearing and cracking by frictional heat, and a method of manufacturing the same.
  • One aspect of the present invention is by weight, C: 0.05 ⁇ 0.10%, Si: 0.01 ⁇ 0.5%, Mn: 1.2 ⁇ 2.0%, Al: 0.01 ⁇ 0.1%, Cr: 0.005 ⁇ 0.3%, B: 0.0003 ⁇ 0.0010 %, Mo: 0.005-0.2%, P: 0.001-0.05%, S: 0.001-0.01%, N: 0.001-0.01%, Nb: 0.005-0.08%, Ti: 0.005-0.13%, V: 0.005-0.2%
  • the present invention relates to a high strength cold rolled steel sheet including shear Fe and unavoidable impurities, satisfying the following relations (1) and (2), and having excellent shearing property including at least one of carbide, nitride, and carbonitride.
  • Another aspect of the invention is by weight, C: 0.05-0.10%, Si: 0.01-0.5%, Mn: 1.2-2.0%, Al: 0.01-0.1%, Cr: 0.005-0.3%, B: 0.0003- 0.0010%, Mo: 0.005 to 0.2%, P: 0.001 to 0.05%, S: 0.001 to 0.01%, N: 0.001 to 0.01%, Nb: 0.005 to 0.08%, Ti: 0.005 to 0.13%, V: 0.005 to 0.2 Heating the steel slab containing%, remaining Fe and inevitable impurities, and satisfying the following relations (1) and (2) to 1200 to 1350 ° C; Hot rolling the heated steel slab at a temperature in the range of 850 ° C to 1150 ° C; Cooling and winding to a temperature in the range of 550 to 750 ° C. after the hot rolling; And it relates to a method for producing a high strength cold rolled steel sheet having excellent shear workability comprising the step of cold rolling at 60 ⁇ 70% cold reduction
  • each element symbol represents the weight% of the alloy element.
  • a high strength cold rolled steel sheet having excellent shearing property and a method of manufacturing the same, which can secure high strength and high hardness, and can suppress cracking caused by shearing and cracking caused by frictional heat.
  • 1 is a graph showing the values of relation (1) and relation (2) of the embodiments.
  • the high strength cold rolled steel sheet having excellent shearability according to the present invention is a weight%, C: 0.05 ⁇ 0.10%, Si: 0.01 ⁇ 0.5%, Mn: 1.2 ⁇ 2.0%, Al: 0.01 ⁇ 0.1%, Cr: 0.005 ⁇ 0.3% , B: 0.0003 to 0.0010%, Mo: 0.005 to 0.2%, P: 0.001 to 0.05%, S: 0.001 to 0.01%, N: 0.001 to 0.01%, Nb: 0.005 to 0.08%, Ti: 0.005 to 0.13%, V: 0.005-0.2%, remaining Fe and inevitable impurities, satisfying the following relations (1) and (2), and include at least one of carbide, nitride and carbonitride.
  • the C is the most economical and effective element to strengthen the steel, and as the amount added increases the precipitation strengthening effect or the fraction of bainite phase, the tensile strength is increased. If the content is less than 0.05%, the reaction for forming precipitates with Ti, Nb, V and the like is small, and the precipitation strengthening effect is low. On the other hand, when the carbon content exceeds 0.10% by weight, coarse carbides are likely to occur at grain boundaries, and fine shear occurs at coarse carbide interfaces during shearing, resulting in inferior shearing properties. Therefore, the content of C is preferably contained in 0.05 to 0.10% by weight.
  • the Si deoxidizes molten steel and has a solid solution strengthening effect, and is advantageous in improving moldability by delaying coarse carbide formation.
  • the content is less than 0.01%, the effect of delaying the formation of carbides is small, so that it is difficult to improve the formability.
  • the content exceeds 0.5%, the red scale due to Si is formed on the surface of the steel sheet during hot rolling. In addition, there is a problem that the ductility and weldability is also reduced. Therefore, the content of Si is preferably contained in 0.01 ⁇ 0.5%.
  • Mn is an effective element to solidify the steel and increases the hardenability of the steel to facilitate the formation of the bainite phase in the weld heat affected zone after welding.
  • the content is less than 1.2%, the above effect by addition cannot be sufficiently obtained.
  • the content exceeds 2.0%, the hardenability is greatly increased, the ferrite phase transformation is delayed, and the precipitation strengthening effect is also reduced, and the segregation part is greatly developed at the center of thickness during slab casting in the casting process, and when cooled after hot rolling In the non-uniform microstructure in the thickness direction, the occurrence of cracks during shearing is greatly increased. Therefore, the content of Mn is preferably included in 1.2 to 2.0%.
  • the Mo strengthens the steel and increases the hardenability of the steel, thereby increasing the strength of the steel.
  • the content is less than 0.005%, the above effect may not be obtained, and if the content exceeds 0.2%, ferrite phase transformation is delayed due to excessive increase in quenchability, and the precipitation strengthening effect is also reduced. It is also economically disadvantageous and also detrimental to weldability. Therefore, the content of Mo is preferably limited to 0.01 ⁇ 0.2%.
  • the Cr increases the strength of the steel by solidifying the steel and increasing the hardenability of the steel. However, if the content is less than 0.005%, the above effect may not be obtained. If the content exceeds 0.3%, the ferrite transformation is excessively delayed, the elongation is inferior to martensite phase formation, and the precipitation strengthening effect is also reduced. In addition, segregation at the center of thickness is greatly developed similarly to Mn, and inferior shear processing property by uneven thickness direction microstructure. Therefore, the content of Cr is preferably limited to 0.005 to 0.3%.
  • B is an element that improves the hardenability even when a small amount is added to the steel.
  • B may be segregated at the austenite grain boundary at high temperature to stabilize the grain boundary and improve impact resistance, but if it is less than 0.0003%, It is not enough to get the effect.
  • the content is added more than 0.0010%, the recrystallization during hot rolling delayed to increase the elongated grains and the ferrite phase transformation during cooling causes the microstructure to be uneven.
  • the precipitation strengthening effect is also reduced to obtain the desired strength, and the non-uniformity of the initial hot rolled plate microstructure is a disadvantage in the present invention because it causes local stress concentration during cold rolling. Therefore, the content of B is preferably limited to 0.0003 ⁇ 0.0010%.
  • P has a solid solution strengthening effect and a ferrite transformation promoting effect.
  • it is economically disadvantageous to manufacture the content to less than 0.001%, and it is economically disadvantageous and insufficient to obtain strength. If the content exceeds 0.05%, brittleness due to intergranular segregation occurs and fine cracking occurs during shearing. It is easy to do and deteriorates ductility and impact resistance significantly. Therefore, the P is preferably limited to 0.001 to 0.05%.
  • S is an impurity present in steel, and if its content exceeds 0.01%, it combines with Mn to form a non-metallic inclusion. Therefore, when the steel is cut, fine cracks are likely to occur and the elongation flange and impact resistance are greatly reduced. In addition, in order to manufacture less than 0.001%, the steelmaking industry takes a lot of time and productivity is reduced. Therefore, it is preferable to limit the content to 0.001 to 0.01%.
  • Al is a component mainly added for deoxidation. If the content is less than 0.01%, the addition effect is insufficient. On the other hand, if the content exceeds 0.1%, AlN is formed by combining with nitrogen, which is likely to cause corner cracks in the slab during casting, and defects due to inclusions are easily generated at edges of the hot rolled sheet. In addition, there may be a problem that the surface quality is lowered due to the occurrence of surface defects during cold rolling after hot rolling. Therefore, it is preferable to limit the content to 0.01 to 0.1%.
  • N is a representative solid solution strengthening element together with C to form coarse precipitates together with Ti, Al and the like.
  • the solid solution strengthening effect of N is better than carbon, but the problem of toughness is greatly reduced as the amount of N in the steel increases.
  • it is preferable to limit the content to 0.001 to 0.01%.
  • Ti is a representative precipitation enhancing element and forms coarse TiN in steel with strong affinity with N.
  • TiN has an effect of suppressing grain growth during heating for hot rolling.
  • Ti remaining after reacting with nitrogen is dissolved in carbon to bond with carbon to form TiC precipitates, which is a useful component for improving the strength of steel. Therefore, if the Ti content is less than 0.005%, the above effect cannot be obtained. If the Ti content exceeds 0.13%, there is a problem of inferior shear workability during shear processing due to the generation of coarse TiN. Therefore, in the present invention, it is preferable to limit the content to 0.005 to 0.13%.
  • Nb is a representative precipitation enhancing element, and is precipitated during hot rolling, and is effective in improving the strength and impact toughness of the steel by refining grains by delaying recrystallization.
  • the Nb content is less than 0.005%, the above effect cannot be sufficiently obtained.
  • the Nb content exceeds 0.08%, the shearability is inferior due to the formation of stretched grains and coarse composite precipitates due to excessive recrystallization during hot rolling. There is a problem to let. Therefore, in the present invention, it is preferable to limit the content to 0.005 ⁇ 0.08%.
  • V is a representative precipitation strengthening element together with Nb and Ti, and is effective in improving the strength of steel by forming a precipitate after winding. Therefore, if the content of V is less than 0.005%, the above effects cannot be sufficiently obtained. If the content of V is more than 0.2%, the shear workability is inferior due to the formation of coarse complex precipitates, and it is economically disadvantageous. Therefore, in the present invention, it is preferable to limit the content to 0.005 to 0.2%.
  • the remaining component of the present invention is iron (Fe).
  • impurities which are not intended from the raw material or the surrounding environment may be inevitably mixed, and thus cannot be excluded. Since these impurities are known to those skilled in the art, all of them are not specifically mentioned in the present specification.
  • the alloy composition must satisfy the following relations (1) and (2) to uniformly form the microstructure of the steel after hot rolling to suppress cracking during shearing after cold rolling.
  • each element symbol represents the weight% of the alloy element.
  • the relation (1) is related to the hardenability and segregation of the steel, taking into account the effect of strengthening the solid solution of the steel and the nonuniformity of the microstructure.
  • the relation (1) is less than 2.0, there is a problem that a sufficient high strength is not obtained because the solid solution strengthening effect of the steel is insufficient. On the other hand, if the relation (1) exceeds 2.5, there is a problem that the microstructure in the thickness direction of the steel is formed non-uniformly, delaying the ferrite phase transformation to reduce the precipitation strengthening effect of the steel.
  • relation (1) may be 2.0-2.5.
  • the relation (2) restricts the components related to the formation of precipitates in the steel, and since the formation of the precipitates is correlated with the contents of Ti, Nb, V, C, and N in the composition, the addition amount of Ti, Nb, and V alloy elements is defined as C, It is intended to set according to the content of N.
  • the relation (2) is less than 0.2, the precipitation strengthening effect is significantly reduced, and thus the desired strength and hardness value cannot be obtained. If the ratio exceeds 0.5, the yield strength is greatly increased due to the formation of a large amount of fine precipitates. There is a problem that the precipitate is formed non-uniformly in the direction of the plate thickness, so that the occurrence of cracks during shearing after cold rolling is severe.
  • relation (2) may be 0.2-0.5.
  • the cold rolled steel sheet according to the present invention is obtained by cold rolling a hot rolled sheet having a microstructure of ferrite and fine perlite, and thus has a microstructure (Full Hard microstructure) that is severely deformed in the rolling direction. At this time, each phase cannot be specified in the microstructure of the cold rolled steel sheet.
  • the hot rolled steel sheet before cold rolling has an area fraction of more than 90%, a fine pearlite phase of less than 5%, and other bainite phases. Can be included.
  • the high strength cold rolled steel sheet having excellent shearability according to the present invention includes at least one of carbide, nitride and carbonitride.
  • carbide nitride and carbonitride.
  • the average size of the carbide, nitride and carbonitride is preferably 10 ⁇ 50nm.
  • the yield strength of the hot rolled sheet is excessively increased, so that local work hardening deviation occurs easily during cold rolling, and cracks occur during shearing and heat treatment of the cold rolled sheet.
  • the cold rolled steel sheet may have a tensile strength of 1200 MPa or more and a hardness value (Micro-Vickers) of 340 Hv or more. By satisfying the tensile strength and the hardness value, it can be preferably applied to the friction plate of the automobile automatic transmission.
  • the crack generated during the shearing of the cold rolled steel sheet preferably has a maximum crack length of 1 mm or less.
  • the maximum crack length is a result of measuring the maximum crack length in the cross section after punching under a condition of Clearance 6% using a circular mold having a diameter of 10 mm, followed by heat treatment at 200 ° C. for 1 hour.
  • the crack generation amount is increased and the crack can be easily propagated during shearing, and if the temperature rises by frictional heat, the crack can be more easily propagated.
  • a method of manufacturing a high strength cold rolled steel sheet having excellent shearing property includes heating a steel slab satisfying the above-described alloy composition to 1200 to 1350 ° C .; Hot rolling the heated steel slab at a temperature in the range of 850 ° C to 1150 ° C; Cooling and winding to a temperature in the range of 550 to 750 ° C. after the hot rolling; And pickling after the winding to cold roll at a cold reduction rate of 60 to 70%.
  • the steel slab that satisfies the alloy composition described above is heated to 1200 to 1350 ° C.
  • the reheating temperature is preferably limited to 1200 to 1350 ° C.
  • the steel slab may be produced in a process in which the continuous casting process and the hot rolling process are directly connected.
  • the continuous casting process and the hot rolling process as described above can be preferably applied to the process directly connected.
  • the heated steel slabs are hot rolled at a temperature in the range of 850-1150 ° C.
  • Initiating hot rolling at a temperature higher than 1150 ° C. increases the temperature of the hot rolled steel sheet, resulting in coarse grain size and inferior surface quality of the hot rolled steel sheet.
  • the hot rolling is terminated at a temperature lower than 850 ° C., the development and high yield ratio of the stretched grains may be attained due to excessive recrystallization delay, resulting in inferior cold rolling and poor shearing properties.
  • the bainite phase and martensite phase in the steel are formed, and the material of the steel may become thermally damaged. If it is wound up to more than 750 °C, coarse ferrite grains are formed and coarse carbide and nitride are formed. It can become easy and the material of steel may be inferior.
  • the average cooling rate is less than 10 °C / sec during cooling coarse ferrite grains are formed may be a non-uniform microstructure, if the average cooling rate is more than 70 °C / sec, bainite phase is easily formed and the thickness direction of the plate
  • the microstructure into the furnace may also be non-uniform, leading to inferior shearing workability of the steel.
  • the cold reduction ratio is less than 60%, it is difficult to obtain sufficient work hardening effect and thus it is difficult to secure the strength and hardness of the steel.
  • the cold reduction rate exceeds 70%, the edge quality of the steel is deteriorated, and the shear workability may be inferior.
  • the cold rolled steel sheet manufactured by the above-described manufacturing method can secure high strength and high hardness, as well as suppress cracking caused by shearing and cracking caused by frictional heat.
  • the cold rolled steel sheet produced by the above production method includes at least one of carbide, nitride and carbonitride, the average size of the carbide, nitride and carbonitride may be 10 ⁇ 50nm.
  • the tensile strength is 1200MPa or more and the hardness value may be more than 340Hv, cracks generated during shearing may have a maximum crack length of 1mm or less.
  • the steel slab having the component composition shown in Table 1 below was heated to 1250 ° C, and a cold rolled steel sheet was manufactured by applying the production conditions shown in Table 2 below. At this time, the cooling rate after the hot rolling was set to 20 ⁇ 30 °C / sec.
  • Table 3 shows the mechanical properties and microstructure observation results of the invention and comparative examples.
  • TS, Hv, and the maximum crack length mean the tensile strength and micro-ickers hardness value of the cold rolled sheet, respectively, and the maximum crack length was punched under the condition of Clearance 6% using a circular mold having a diameter of 10 mm, and then 200 ° C. This is the result of measuring the maximum crack length in cross section after heat treatment for 1 hour at. The length of the cracks was measured from the results of observation of optical magnification 100 times.
  • the size of carbides, nitrides and carbonitrides formed in steel were analyzed for hot rolled plates before cold rolling.
  • Carbide, nitride and carbonitride with an average size of 10 ⁇ 50nm formed in steel are not changed in size and fraction by cold rolling, and it is difficult to accurately observe the size and fraction in the microstructure that is severely deformed after cold rolling.
  • the hot rolled plate was analyzed.
  • the average size of carbides, nitrides and carbonitrides was determined from the results measured using a transmission electron microscope.
  • the measurement of carbides and nitrides with an average size of 100 nm or more was used for the measurement of 50,000 magnification, and the results of 100,000 magnifications were used for precipitates with an average size of less than 100 nm.
  • the tensile test was taken as the test piece collected based on JIS5 standard based on 0 degree direction with respect to the rolling direction of a rolled sheet material.
  • Comparative Examples 1 and 2 did not satisfy both the relational formula (1) and the relational formula (2), and Comparative Example 1 did not satisfy the C content. Both comparative examples did not achieve sufficient solid solution effect, and exceeded the upper limit of relation (2) due to relatively low C content and relatively excessive Ti, Nb, and V. Therefore, the size of carbon, nitride and precipitates formed in the steel was fine, but the strength of the steel was not sufficiently secured.
  • Comparative Example 2 as a result of giving the cold reduction ratio exceeding the range controlled in the present invention, it can be confirmed that the cracks in the shearing surface after the punching process occurs slightly worse, the quality of the shearing surface is inferior.
  • Comparative Examples 3 and 5 did not satisfy the relational expression (1).
  • Comparative Example 3 segregation was increased at the center of the steel beyond the scope of the relational expression (1).
  • Comparative Example 5 had a low Mn, Cr, B content and the like, segregation was less, so the quality of the shearing surface was very good, but sufficient solid-solution strengthening effect was not obtained, so that the target strength and hardness could not be obtained.
  • Comparative Examples 4 and 6 did not satisfy the relation (2).
  • Comparative Example 4 surplus C remained to form coarse precipitates and carbides, and the precipitation strengthening effect was insufficient to obtain the target strength and hardness values. It was.
  • Comparative Example 6 a large amount of fine precipitates were formed in excess of the scope of the formula (2) and high strength was obtained, but cracks were severe in the shear processing part.
  • Comparative Examples 7, 8, 9 and 10 are steels manufactured for the purpose of tensile strength of 1350 MPa or more and hardness value of 355 Hv or more after cold rolling. Comparative Example 7 does not satisfy the relational formula 1, but has high cold rolling properties. Secured. However, due to the high cold rolling rate, cracking was more severe in the shearing part.

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Abstract

Sous un aspect, la présente invention concerne une tôle d'acier haute résistance laminée à froid ayant une excellente aptitude au traitement sous cisaillement, la tôle comprenant, en pourcentage pondéral, de 0,05 à 0,10 % de C, de 0,01 à 0,5 % de Si, de 1,2 à 2,0 % de Mn, de 0,01 à 0,1 % d'Al, de 0,005 à 0,3 % de Cr, de 0,0003 à 0,0010 % de B, de 0,005 à 0,2 % de Mo, de 0,001 à 0,05 % de P, de 0,001 à 0,01 % de S, de 0,001 à 0,01 % de N, de 0,005 à 0,08 % de Nb, de 0,005 à 0,13 % de Ti, de 0,005 à 0,2 % de V, le reste étant constitué de Fe et des impuretés inévitables, et ladite tôle satisfaisant aux relations suivantes (1) et (2) et contenant au moins un carbure, un nitrure et un carbonitrure. Relation (1) : 2,0 ≤ [Mn] +2,5 [Mo] + 1,5 [Cr] +300 [B] ≤ 2,5 Relation (2) : 0,2 ≤ ([Nb]/93 + [Ti]/48 + [V] /51) / ([C]/12 + [N]/14) ≤ 0,5 (Dans les relations (1) et (2), chaque symbole d'élément représente le pourcentage pondéral de l'élément d'addition correspondant. )
PCT/KR2016/013362 2015-11-20 2016-11-18 Tôle d'acier haute résistance laminée à froid ayant une excellente aptitude au traitement sous cisaillement, et son procédé de fabrication Ceased WO2017086745A1 (fr)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3964600A4 (fr) * 2019-05-03 2022-06-22 Posco Feuille d'acier très haute résistance offrant une excellente ouvrabilité de cisaillement et son procédé de fabrication

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102328392B1 (ko) 2019-12-20 2021-11-19 주식회사 포스코 펀칭 가공부 단면품질이 우수한 초고강도 강판 및 그 제조방법
KR102438481B1 (ko) * 2020-12-21 2022-09-01 주식회사 포스코 가공성이 우수한 냉연강판 및 그 제조방법
CN121204544A (zh) * 2024-06-26 2025-12-26 宝山钢铁股份有限公司 横纵向强度差异低的低成本冷轧低合金高强钢及其制造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10130782A (ja) * 1996-11-01 1998-05-19 Nippon Steel Corp 超高強度冷延鋼板およびその製造方法
JP2010285657A (ja) * 2009-06-11 2010-12-24 Nippon Steel Corp 析出強化型複相冷延鋼板及びその製造方法
KR20140117567A (ko) * 2012-02-13 2014-10-07 신닛테츠스미킨 카부시키카이샤 냉연 강판, 도금 강판 및 그들의 제조 방법
JP2015034334A (ja) * 2013-07-12 2015-02-19 株式会社神戸製鋼所 めっき性、加工性、および耐遅れ破壊特性に優れた高強度めっき鋼板、並びにその製造方法
KR20150075321A (ko) * 2013-12-25 2015-07-03 주식회사 포스코 형상 품질이 우수한 초고강도 냉연강판 및 그 제조방법

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4730056B2 (ja) * 2005-05-31 2011-07-20 Ｊｆｅスチール株式会社 伸びフランジ成形性に優れた高強度冷延鋼板の製造方法
JP4858286B2 (ja) 2007-04-20 2012-01-18 住友金属工業株式会社 フルハード冷延鋼板
JP5245777B2 (ja) * 2008-12-05 2013-07-24 新日鐵住金株式会社 フルハード冷延鋼板
KR101228753B1 (ko) * 2010-12-07 2013-01-31 주식회사 포스코 형상 품질이 우수한 초고강도 냉연강판 및 그 제조방법
JP5182386B2 (ja) * 2011-01-31 2013-04-17 Ｊｆｅスチール株式会社 加工性に優れた高降伏比を有する高強度冷延鋼板およびその製造方法
JP5725909B2 (ja) 2011-02-28 2015-05-27 日新製鋼株式会社 耐摩耗性に優れたクラッチプレート用鋼板およびその製造方法
JP5834717B2 (ja) * 2011-09-29 2015-12-24 Ｊｆｅスチール株式会社 高降伏比を有する溶融亜鉛めっき鋼板およびその製造方法
DE102012002079B4 (de) * 2012-01-30 2015-05-13 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines kalt- oder warmgewalzten Stahlbandes aus einem höchstfesten Mehrphasenstahl
JP5633594B2 (ja) * 2013-04-02 2014-12-03 Ｊｆｅスチール株式会社 打ち抜き性および耐熱ひずみ特性に優れた冷延鋼板およびその製造方法
JP6119627B2 (ja) * 2014-02-05 2017-04-26 Ｊｆｅスチール株式会社 比例限の高い高強度冷延薄鋼板およびその製造方法
JP6292001B2 (ja) * 2014-04-25 2018-03-14 新日鐵住金株式会社 フルハード冷延鋼板

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10130782A (ja) * 1996-11-01 1998-05-19 Nippon Steel Corp 超高強度冷延鋼板およびその製造方法
JP2010285657A (ja) * 2009-06-11 2010-12-24 Nippon Steel Corp 析出強化型複相冷延鋼板及びその製造方法
KR20140117567A (ko) * 2012-02-13 2014-10-07 신닛테츠스미킨 카부시키카이샤 냉연 강판, 도금 강판 및 그들의 제조 방법
JP2015034334A (ja) * 2013-07-12 2015-02-19 株式会社神戸製鋼所 めっき性、加工性、および耐遅れ破壊特性に優れた高強度めっき鋼板、並びにその製造方法
KR20150075321A (ko) * 2013-12-25 2015-07-03 주식회사 포스코 형상 품질이 우수한 초고강도 냉연강판 및 그 제조방법

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3964600A4 (fr) * 2019-05-03 2022-06-22 Posco Feuille d'acier très haute résistance offrant une excellente ouvrabilité de cisaillement et son procédé de fabrication
US12509742B2 (en) 2019-05-03 2025-12-30 Posco Co., Ltd Ultra-high strength steel sheet having excellent shear workability and method for manufacturing same

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