WO2007007983A1 - Tôle d’acier pour emboutissage profond présentant une excellente résistance à la fragilisation par le réusinage et d’excellentes propriétés en matière de fatigue et de placage, et son procédé de fabrication - Google Patents

Tôle d’acier pour emboutissage profond présentant une excellente résistance à la fragilisation par le réusinage et d’excellentes propriétés en matière de fatigue et de placage, et son procédé de fabrication Download PDF

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Publication number
WO2007007983A1
WO2007007983A1 PCT/KR2006/002657 KR2006002657W WO2007007983A1 WO 2007007983 A1 WO2007007983 A1 WO 2007007983A1 KR 2006002657 W KR2006002657 W KR 2006002657W WO 2007007983 A1 WO2007007983 A1 WO 2007007983A1
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WIPO (PCT)
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steel sheet
steel
properties
rolling
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PCT/KR2006/002657
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English (en)
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WO2007007983A9 (fr
Inventor
Hee-Jae Kang
Kwang-Keun Chin
Sang-Ho Han
Chang-Sik Choi
Original Assignee
Posco
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Filing date
Publication date
Application filed by Posco filed Critical Posco
Priority to US11/994,630 priority Critical patent/US20080196799A1/en
Priority to AT06769200T priority patent/ATE550448T1/de
Priority to JP2008520188A priority patent/JP4848423B2/ja
Priority to CN2006800250138A priority patent/CN101218363B/zh
Priority to EP06769200A priority patent/EP1920078B1/fr
Publication of WO2007007983A1 publication Critical patent/WO2007007983A1/fr
Publication of WO2007007983A9 publication Critical patent/WO2007007983A9/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

  • the present invention relates to steel sheets for deep drawing mainly used for interior or exterior plates of automobile bodies, and the like. More particularly, the present invention relates to steel sheets for deep drawing, which have a tensile strength of 28 ⁇ 50 Df/D while exhibiting excellent secondary work embrittlement resistance, fatigue properties of welded joints, and plating properties as well as excellent formability, and to a method for manufacturing the same.
  • steel sheets for the automobile body have been required to have further enhanced formability.
  • the steel sheets for the automobile body also have been required to have excellent secondary work embrittlement and fatigue properties of welded joints in terms of using conditions of the automobiles, and to have an appealing plated surface.
  • steel sheets having enhanced formability and strength are produced in such a way of adding formability enhancing elements, that is, carbide and nitride formation elements such as Ti, Nb and the like, and strength enhancing elements, that is, solid solution strengthening elements such as Mn, P, Si and the like to a highly pure steel which is minimized in contents of impurities in the steel. Due to inherent restrictions in properties of the steel, however, it is difficult to enhance the formability and the strength at the same time.
  • formability enhancing elements that is, carbide and nitride formation elements such as Ti, Nb and the like
  • strength enhancing elements that is, solid solution strengthening elements such as Mn, P, Si and the like
  • the steel sheets for deep drawing are produced using, so called, ultra-low carbon interstitial free (IF) steel, which is produced by adding the carbide and nitride formation elements such as Ti, Nb, and the like as a single component or a combination thereof to ultra- low carbon steel while lowering an amount of interstitial solid solution elements such as C or N to 50 ppm or less during a steel making process in order to ensure good formability.
  • IF ultra-low carbon interstitial free
  • the carbide and nitride formation elements such as Ti, Nb, and the like are added in an amount of 0.01 ⁇ 0.07% to the ultra-low carbon steel in order to ensure workability
  • the steel lacks in the interstitial solid solution strengthening elements which serve to strengthen the grain boundaries, causing the secondary work embrittlement while deteriorating the fatigue properties at the spot welded joints.
  • inventors of the present invention invented a high strength steel sheet for extra deep drawing useful for automobiles and the like, and a method for manufacturing the same disclosed in Korean Patent Laid-open Publication No. 2004-0002768, which comprises, by weight%, C: 0.010% or less, Si: 0.02% or less, Mn: 1.5% or less, P: 0.03 ⁇ 0.15%, S: 0.02% or less, Sol.
  • the present invention has been made to solve the above problems, and it is an object of the present invention to provide a high strength steel sheet for deep drawing, which is controlled in contents of Ti, Al, B and N, and in contents of Nb, Al and C combinationally, while increasing the content of Al, which is advantageous in terms of formability and plating properties, and reducing the content of Ti, which is disadvantageous in terms of the plating properties, and the like, thereby providing excellent properties in terms of secondary work embrittlement resistance, and fatigue properties of welded joints as well as formability while exhibiting an appealing surface quality.
  • a high strength steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties, comprising, by weight%: C: 0.010% or less, Si: 0.02% or less, Mn: 0.06 ⁇ 1.5%, P: 0.15% or less, S: 0.020% or less, Sol.
  • Al 0.10 ⁇ 0.40%, N: 0.010% or less, Ti: 0.003 ⁇ 0.010%, Nb: 0.003 ⁇ 0.040%, B: 0.0002 ⁇ 0.0020%, and the balance of Fe and other unavoidable impurities, wherein the composition of Ti, Al, B, and N satisfies the relationship: 1.0 ⁇ (Ti[%]+Al[%]/16+6B[%])/3.43N[%] ⁇ 4.1, and wherein the composition of Nb, Al, and C satisfies the relationship: 0.7 ⁇ (Nb[%]+Al[%] / 20)/7.75C[%] ⁇ 3.5.
  • a method for manufacturing a high strength steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties comprises: reheating a steel slab at a temperature of 1,100 ⁇ 1,250 0 C, the steel slab comprising, by weight%: C: 0.010% or less, Si: 0.02% or less, Mn: 0.06 ⁇ 1.5%, P: 0.15% or less, S: 0.020% or less, Sol.
  • the steel sheets for deep drawing according to the present invention exhibit excellent secondary work embrittlement, fatigue properties of welded joints, and an appealing plated surface as well as excellent formability compared with the conventional high strength steel sheets for deep drawing.
  • a high strength steel sheet according to the present invention has characteristics in that it is controlled in contents of Ti, Al, B and N, and in contents of Nb, Al and C combinationally, while increasing the content of Al, which is advantageous in terms of formability and plating properties, and reducing the content of Ti, which is disadvantageous in terms of the plating properties, and the like, thereby exhibiting excellent properties in terms of secondary work embrittlement resistance, fatigue properties of welded joints and plating properties as well as formability.
  • carbon content exceeds 0.010%, it is necessary to increase the contents of Ti and Nb which are carbide and nitride formation elements, causing a disadvantage in terms of manufacturing costs.
  • the carbon content is preferably 0.010% or less.
  • Si is an element which causes a defect of surface scale. If silicon content exceeds
  • the silicon content is preferably 0.02% or less.
  • Mn is a substitutional solid solution strengthening element for ensuring strength.
  • Mn content is less than 0.06%, the steel suffers from embrittlement due to S in the steel, whereas, if the Mn content exceeds 1.5%, an r- value of the steel is rapidly deteriorated along with elongation.
  • the Mn content is preferably in the range of 0.06 ⁇ 1.5%.
  • P is also a representative solid solution strengthening element which is added to the steel along with Mn for increasing the strength.
  • P is added to Ti-Nb added steel as in the steel of the present invention, it results in growth of the ⁇ 111 ⁇ texture, advantageous in terms of the r- value, through grain refinement, grain boundary segregation, and the like.
  • P content exceeds 0.15%, the steel suffers from rapid reduction in elongation along with significant increase in brittleness.
  • the P content is preferably in the range of 0.15% or less.
  • S content in the steel is generally restricted to a low degree of 0.005% or less. According to the present invention, however, since the steel contains Mn, all amounts of S in the steel are precipitated as MnS, thereby enabling deterioration of formability due to solid solution S to be avoided.
  • S content is preferably 0.020% or less, which deviates from a region causing edge cracks during rolling.
  • Sol. Al content of the steel is generally controlled to be in the range of 0.02 ⁇ 0.07% while dissolved oxygen in the steel is maintained in a sufficiently low state in consideration of manufacturing costs.
  • Sol. Al serves to allow deep drawability to be stably secured at a lower annealing temperature.
  • Sol. Al diffuses to the surface of the steel along the grain boundaries, and makes a plated layer dense, thereby enhancing powdering resistance of the steel.
  • the Sol. Al content is 0.10% or more in the steel, it coarsens the precipitates in the steel, remarkably obstructs effect of suppressing recrystallization by P, thereby activating the recrystallization, and aids in development of the ⁇ 111 ⁇ texture and enhancement of the powdering resistance. If the Sol. Al content exceeds 0.40%, it causes an increase of the costs, and deterioration in efficiency of continuous casting operation.
  • the Sol. Al content is preferably in the range of 0.10 ⁇ 0.40%.
  • the Sol. Al content influences formation of Ti or Nb-based precipitates as the carbide and nitride such that the precipitates become coarsened, it serves as a critical component, which provides further enhanced formability of the steel with small added amounts of Ti and Nb in comparison to the conventional IF steel.
  • N generally exists in a solid solution state, and deteriorates the formability of the steel. If N content exceeds 0.010%, it is necessary to increase added amounts of Ti and Nb for fixing N as precipitates. Thus, the N content is preferably 0.010% or less.
  • Ti is a very important element in terms of the formability. In order to provide effect of enhancing the formability (in particular, r- value), Ti must be added to the steel in an amount of 0.003% or more. However, if Ti content exceeds 0.010%, it is disadvantageous in terms of manufacturing costs and plating properties in galvannealing. Thus, the Ti content is preferably in the range of 0.003 ⁇ 0.010%.
  • Nb is also a very important element in terms of the formability like Ti.
  • Nb In order to provide the effect of enhancing the formability (in particular, r- value), Nb must be added to the steel in an amount of 0.003% or more.
  • Nb content exceeds 0.040%, it is disadvantageous in terms of the manufacturing costs and the plating properties.
  • the Nb content is preferably in the range of 0.003 ⁇ 0.040%.
  • B is a grain boundary strengthening element, and effective to enhance fatigue properties of spot welded joints while preventing grain boundary embrittlement by P. If B content is less than 0.0002%, the steel fails to achieve the effect described above, whereas, if the B content exceeds 0.0020%, there arise problems of rapid reduction in the formability, and deterioration in surface properties of plated steel sheet. Thus, the B content is preferably 0.0002 ⁇ 0.0020%.
  • the steel sheet comprises the balance of Fe and other unavoidable impurities in addition to the above components. Additionally, the steel sheet of the present invention may further comprise Mo in order to further enhance the secondary work embrittlement resistance and the plating properties. At this time, Mo content is preferably 0.05% or less. The reason is that, if the Mo content exceeds 0.05%, the effect of enhancing the secondary work embrittlement resistance and the plating properties by the Mo content is significantly reduced, and it is disadvantageous in terms of the manufacturing costs.
  • the present invention in order to simultaneously secure the formability, plating properties, secondary work embrittlement resistance and fatigue properties of the steel which has the composition with a low Ti content and a high Al content as described above, it is necessary to control the contents of Al, B and N in combination to addition of Ti as in the following Expression 1.
  • the present invention since the Ti content is low in comparison to the conventional steel sheet, there is a high possibility of deterioration of formability.
  • the present invention suggests the following Expression 1:
  • the present invention in order to ensure the deep drawability and the stretching properties more stably, it is necessary to control the contents of the components so as to satisfy the following Expression 2. Specifically, due to the low Ti content of the steel according to the present invention, it is necessary to further ensure the deep drawability and the stretching properties. To this end, the present invention controls the contents of Nb, Al and C in combination according to the following Expression 2:
  • Nb-Ti-Al-N-C based composite precipitates are formed.
  • an average size of Nb-Ti-Al-N-C based composite precipitates is controlled to be 40 D or more, it is more preferable since it can further enhance the formability of the steel sheet.
  • the formability and the plating properties can be further enhanced by restricting ° a fraction of Ti A Cl Sl to be 50% or more and a fraction of TiC to be below 5% among the Nb-Ti-Al-N-C based precipitates. Since Ti C S is a precipitate advantageous in terms of the formability and the plating properties desired to be obtained by the present invention, if the fraction of Ti C S is controlled to be 50% or more, it is possible to secure further enhanced formability and plating properties.
  • the steel sheet can be produced to have a desired tensile strength by controlling the components to satisfy the above composition and the following Expression 3:
  • a steel slab having the composition as described above is reheated to a temperature of 1,100 ⁇ 1,250 0 C. If the reheating temperature is less than 1,100 0 C, it is difficult to perform hot rolling, whereas, if the reheating temperature exceeds 1,250 0 C, surface defects can be created.
  • a finish rolling temperature is preferably controlled to be 880 0 C or more. The reason is that, if the finish rolling temperature is less than 880 0 C, mixed grains are created, causing negative properties of products.
  • a ratio of a reduction amount of rough rolling to a reduction amount of finish rolling that is, a reduction amount ratio is suitably controlled during the hot rolling.
  • the reduction amount ratio is preferably controlled in the range of 1.0
  • the increase in reduction amount of the finish rolling b can cause an increase in fraction of Ti A Cl Sl which is ad- vantageous in terms of the formability and the plating properties, and a decrease in fraction of TiC, which is disadvantageous in terms of the plating properties.
  • the reduction amount ratio is restricted due to the following reasons: increasing the reduction amount of the finish rolling serves not only to allow the precipitates mainly having the size of several hundreds of or more to be distributed in the steel sheet without forming the solid solution elements therein, but also to increase the fraction of the precipitate, which is advantageous in terms of the formability and the plating properties, while decreasing the fraction of the precipitate, which is disadvantageous in terms of the plating properties, thereby improving the r-value and the plating properties of the final product.
  • the coil hot-rolled steel sheet is subjected to cold rolling and continuous annealing.
  • a reduction ratio of the cold rolling is preferably restricted to be 65% or more since the reduction ratio below 65% makes it difficult to obtain a high r-value of 1.9 or more.
  • the continuous annealing is preferably performed at a temperature of 780 ⁇ 860 0 C.
  • the cold rolled steel sheet produced as above can be subjected to a typical plating process, if necessary.
  • the plating process may be, for example, galvanizing, gal- vannealing, and the like.
  • the fatigue properties were evaluated under a condition wherein, when applying a load repetitiously a total of ten million times to point welded samples with a cycle of 60 Hz, the samples did not fail.
  • the powdering resistance was evaluated according to a detached ratio of a plated layer due to cupping, which was calculated in terms of a weight ratio.
  • IS Inventive steel
  • CS Comparative steel
  • CA Continuous annealing
  • TS Tensile strength
  • FS Fatigue strength
  • Powdering resistance Reduction in weight of plated layer
  • Comparative steels 1 - 12 not satisfying the conditions of the present invention in terms of composition and relations between the components exhibit de ⁇ teriorated properties in terms of secondary work embrittlement resistance, fatigue properties, and plating properties (powdering resistance) as well as formability compared with the inventive steels.
  • Comparative steels 1, 4, 7 and 10 satisfying the composition according to the present invention while not satisfying the relations between the components, elongation, r-value, secondary work embrittlement resistance and fatigue properties are lower than the inventive steels.
  • Example 2 After reheating steel slabs having the compositions of Inventive Steels 1 and 5 in Table 1 to 1,180 0 C, the steel slabs were subjected to hot rolling with finish rolling at a temperature of 910 0 C, and coiling at a temperature of 650 0 C.
  • a ratio of a reduction amount of rough rolling to a reduction amount of finish rolling was based on the condition as shown in Table 3.
  • the coiled steel sheets were subjected to cold rolling and continuous annealing under the conditions (the conditions of Inventive Steels 1 and 5) shown in Table 2.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

La présente invention décrit une tôle d’acier pour emboutissage profond utilisée dans les automobiles, ainsi que son procédé de fabrication. La tôle d’acier comprend, en % en poids, 0,010 % ou moins de C, 0,02 % ou moins de Si, de 0,06 % à environ 1,5 % de Mn, 0,15 % ou moins de P, 0,020 % ou moins de S, de 0,10 à environ 0,40 % d’Al solide, 0,010 % ou moins de N, de 0,003 à environ 0,010 % de Ti, de 0,003 à environ 0,040 % de Nb, de 0,0002 à environ 0,0020 % de B, et le reste est constitué de Fe et d’autres impuretés inévitables, où la composition de Ti, d’Al, de B et de N satisfait la relation : 1,0 < (Ti [%]+Al [%]/16 + 6B [%])/3,43N [%] < 4,1 et où la composition de Nb, d’Al et de C satisfait la relation : 0,7 < (Nb [%] + Al [%]/20)/7,75C [%] < 3,5. La tôle d’acier présente une excellente résistance à la fragilisation par réusinage, d'excellentes propriétés en matière de fatigue des joints soudés, une surface plaquée attrayante, ainsi qu'une excellente aptitude au formage.
PCT/KR2006/002657 2005-07-08 2006-07-07 Tôle d’acier pour emboutissage profond présentant une excellente résistance à la fragilisation par le réusinage et d’excellentes propriétés en matière de fatigue et de placage, et son procédé de fabrication WO2007007983A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
US11/994,630 US20080196799A1 (en) 2005-07-08 2006-07-07 Steel Sheet for Deep Drawing Having Excellent Secondary Work Embrittlement Resistance, Fatigue Properties and Plating Properties, and Method for Manufacturing the Same
AT06769200T ATE550448T1 (de) 2005-07-08 2006-07-07 Stahlblech zum tiefziehen mit hervorragender beständigkeit gegen verformungsinduzierte versprödung, hervorragenden ermüdungseigenschaften und hervorragenden plattierungseigenschaften und herstellungsverfahren dafür
JP2008520188A JP4848423B2 (ja) 2005-07-08 2006-07-07 耐２次加工脆性、疲労特性及びメッキ特性に優れている深絞り用薄鋼板及びその製造方法
CN2006800250138A CN101218363B (zh) 2005-07-08 2006-07-07 用于深冲的具有极好的抗二次加工脆化性、耐疲劳性和镀敷性能的钢板及其制造方法
EP06769200A EP1920078B1 (fr) 2005-07-08 2006-07-07 Tôle d acier pour emboutissage profond présentant une excellente résistance à la fragilisation par le réusinage et d excellentes propriétés en matière de fatigue et de placage, et son procédé de fabrication

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2005-0061691 2005-07-08
KR1020050061691A KR100685030B1 (ko) 2005-07-08 2005-07-08 내2차가공취성, 피로특성 및 도금특성이 우수한 심가공용박강판 및 그 제조방법

Publications (2)

Publication Number Publication Date
WO2007007983A1 true WO2007007983A1 (fr) 2007-01-18
WO2007007983A9 WO2007007983A9 (fr) 2010-09-16

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PCT/KR2006/002657 WO2007007983A1 (fr) 2005-07-08 2006-07-07 Tôle d’acier pour emboutissage profond présentant une excellente résistance à la fragilisation par le réusinage et d’excellentes propriétés en matière de fatigue et de placage, et son procédé de fabrication

Country Status (7)

Country Link
US (1) US20080196799A1 (fr)
EP (1) EP1920078B1 (fr)
JP (1) JP4848423B2 (fr)
KR (1) KR100685030B1 (fr)
CN (1) CN101218363B (fr)
AT (1) ATE550448T1 (fr)
WO (1) WO2007007983A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
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US8398786B2 (en) 2005-10-06 2013-03-19 Posco Precipitation hardening cold rolled steel sheet having excellent yield ratios, and the method for manufacturing the same
EP4261321A4 (fr) * 2020-12-11 2024-05-29 Posco Co Ltd Feuille d'acier recuite par galvanisation à haute résistance présentant une excellente résistance au poudrage et son procédé de fabrication

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5765080B2 (ja) * 2010-06-25 2015-08-19 Ｊｆｅスチール株式会社 伸びフランジ性に優れた高強度熱延鋼板およびその製造方法
CN102912226A (zh) * 2012-10-17 2013-02-06 首钢总公司 一种抗二次加工脆性dc06汽车用钢及其生产方法
CN106191368B (zh) * 2015-04-30 2018-06-26 上海梅山钢铁股份有限公司 一种高铝超低钛钢水的生产方法

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ATE550448T1 (de) 2012-04-15
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WO2007007983A9 (fr) 2010-09-16
EP1920078A1 (fr) 2008-05-14
US20080196799A1 (en) 2008-08-21
EP1920078B1 (fr) 2012-03-21
JP4848423B2 (ja) 2011-12-28
KR100685030B1 (ko) 2007-02-20
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