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WO2007142197A1 - Feuille d'acier composite à résistance élevée dotée d'excellentes aptitude au moulage et résistance à la fracture différée - Google Patents

Feuille d'acier composite à résistance élevée dotée d'excellentes aptitude au moulage et résistance à la fracture différée Download PDF

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Publication number
WO2007142197A1
WO2007142197A1 PCT/JP2007/061301 JP2007061301W WO2007142197A1 WO 2007142197 A1 WO2007142197 A1 WO 2007142197A1 JP 2007061301 W JP2007061301 W JP 2007061301W WO 2007142197 A1 WO2007142197 A1 WO 2007142197A1
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WO
WIPO (PCT)
Prior art keywords
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steel sheet
strength
ferrite
delayed fracture
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.)
Ceased
Application number
PCT/JP2007/061301
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English (en)
Japanese (ja)
Inventor
Michiharu Nakaya
Yoichi Mukai
Koichi Sugimoto
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Kobe Steel Ltd
Shinshu TLO Co Ltd
Original Assignee
Kobe Steel Ltd
Shinshu TLO Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Kobe Steel Ltd, Shinshu TLO Co Ltd filed Critical Kobe Steel Ltd
Priority to GB0900057.1A priority Critical patent/GB2452230B/en
Priority to CN2007800208296A priority patent/CN101460646B/zh
Priority to US12/303,566 priority patent/US20100221138A1/en
Publication of WO2007142197A1 publication Critical patent/WO2007142197A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention has, for example, a tensile strength of 980 MPa or higher, excellent formability, anti-delayed fraction property, and spot weldability, and is a structural member for automobiles (pillars, members).
  • the present invention relates to a high-strength composite steel sheet useful as body frame members such as reinforcements, bumpers, door guard bars, seat parts, suspension parts, and other reinforcing members.
  • Non-Patent Document 1 high strength is ensured by using a composite structure in which the metal structure is a bainitic ferrite main body and lath-type retained austenite.
  • a steel sheet having improved hole expansibility that is, stretch flangeability
  • TS X E1 is an indicator of strength (TS) 'ductility (E1), and is 9000-10300. That's not true.
  • the maximum heating temperature in a mass production line of actual operation using a continuous annealing furnace is about 900 ° C, and the heating time is 5 minutes or less.
  • 950 After annealing at C for 1200 seconds, 350-400 in a salt bath. It is required to cool down to C and is not suitable for actual operation.
  • Patent Document 1 discloses that the matrix is composed mainly of vinylic ferrite and contains 3% or more of retained austenite, while maintaining a tensile strength of 980 MPa class or higher while maintaining elongation ( E1) is about 20%, and stretch flangeability ( ⁇ ) is 55%.
  • E1 tensile strength
  • ⁇ stretch flangeability
  • this technology requires the addition of expensive alloying elements such as Mo, Ni, and Cu, leaving room for improvement in terms of cost.
  • Patent Document 2 obtains a high level of elongation and stretch flangeability by setting the matrix structure to tempered martensite and ferrite and the retained austenite to have a space factor of 5 to 30%.
  • the microstructure before annealing is important. Therefore, is it possible to perform continuous annealing after taking in an appropriate metal structure by performing low temperature cutting in the hot rolling process? It is necessary to perform continuous annealing at least twice.
  • the structure before annealing cannot be obtained unless the cold rolling rate is kept low, and the intended metal structure cannot be obtained.
  • Significant restrictions are added.
  • continuous annealing is performed twice, although there are no restrictions such as sheet thickness, the number of processes is increased compared to the conventional method, so an increase in cost cannot be avoided.
  • Patent Document 3 discloses a steel sheet having a total phase structure and a stretch flangeability improved by making the matrix structure mainly tempered bainite. This steel grade is being studied mainly with a tensile strength of 900MPa class or less, and therefore, the delayed fracture, which is a particular problem at 980MPa class and above, is carefully considered.
  • Non-Patent Document 1 ISIJ International, Vol.40 (2000), No.9.p920-926
  • Patent Document 1 Japanese Unexamined Patent Application Publication No. 2004-332099
  • Patent Document 2 JP 2003-171735 A Patent Document 3: Japanese Patent Laid-Open No. 2002-309334
  • the present invention has been made in view of the prior art as described above.
  • the purpose of the present invention is to provide a 980 MPa class useful as a structural part for automobiles and the like without adding expensive alloy elements such as Mo, Ni and Cu.
  • the high-strength composite steel sheet of the present invention that has solved the above-mentioned problems is: C: 0.12 to 0.25%, Si: 1.0 to 3.0%, Mn: 1.5 to 3.0%, P: 0.15 % (Less than 0%), S: not more than 0.02% (not including 0%), A1: not more than 0.4% (not including 0%), the balance being iron and inevitable impurities
  • the content of Si, Al, Mn satisfies the relationship of the following formula (I),
  • C 0.12-0.25%
  • Si l.0-3.0%
  • Mn l.5-3.0%
  • Cr l.0% or less
  • P 0.15% or less (0 %)
  • S 0.02% or less (excluding 0%)
  • A1 0.4% or less (excluding 0%)
  • the content of Si, Al, Mn, Cr satisfies the relationship of the following formula ( ⁇ ),
  • microstructure of the longitudinal section is the space factor for the entire structure
  • Average particle size of polygonal ferrite 10 zm or less
  • Residual austenite 5. /. more than
  • the composite steel sheet according to the present invention may include Ti: 0.15% or less (including 0%) and / or Nb: 0.1% or less (including 0%) in addition to the above elements as necessary. Contains Alternatively, as another element, Ca: 30 ppm or less (not including 0%) and / or REM: 30 ppm or less (not including 0%) may be included.
  • the high strength composite steel sheet of the present invention preferably has a tensile strength of 980 MPa or more in order to make effective use of its excellent strength.
  • the chemical composition of the steel material is specified as described above, and in particular, the (Si + Al) ZMn ratio or the (Si + Al) / (Mn + Cr) ratio is controlled within a specific range.
  • the metal structure a composite structure mainly composed of vinylite ferrite (BF) and containing polygonal ferrite (PF) and retained austenite (residual ⁇ ), while maintaining a tensile strength of, for example, a level of 980 MPa or more, and It is possible to provide a low-cost composite steel sheet with good formability (stretch-stretch flangeability) and excellent strength, spot weldability, and delayed fracture resistance.
  • FIG. 1 is an explanatory view showing a heat pattern of heat treatment employed in an experimental example.
  • the first is that elongation is remarkably improved when a certain amount of fine polygonal ferrite is mixed in a structure mainly composed of vinylic ferrite.
  • the ferrite to be mixed is fine, deterioration of strength and stretch flangeability can be suppressed, and the structure should exhibit excellent performance in delayed fracture resistance.
  • C is an element that is indispensable for ensuring high strength and ensuring residual ⁇ , and is important for ensuring that a sufficient amount of C is contained in the ⁇ phase and that the desired amount of ⁇ phase remains at room temperature. Element. In order to exert such an action effectively, it is necessary to contain C in an amount of 0.1% or more, preferably 0.12% or more, more preferably 0.15% or more. However, if the amount of C is too large, there will be a noticeable adverse effect on spot weldability, so the upper limit was set to 0.25% from the viewpoint of ensuring spot weldability. Preferably it is 0.23% or less, more preferably 0.20% or less.
  • Si is an essential element for suppressing the formation of carbides by decomposition of residual ⁇ , and in order to effectively exert these effects.
  • 1.0% or more should be contained, and preferably 1.2% or more should be contained.
  • these effects saturate at 3.0%, and if it exceeds this level, it causes troubles such as spot weldability deterioration and hot brittleness, so at most 3.0% or less, preferably 2.5 It is better to keep it below%.
  • ⁇ is an element that is necessary to suppress the formation of excessive polygonal ferrite and to make a microstructure mainly composed of venetic ferrite. Further, it is an important element for stabilizing ⁇ and securing the desired residual ⁇ , and it is preferable to contain at least 1.5% or more, preferably 2.0% or more. [0026] However, since excessive additive deterioration deteriorates the resistance to delayed fracture when spot weldability is reached, at most
  • A1 is a useful element to suppress the formation of carbides and secure residual ⁇ . If too much is used, polygonal ferrite tends to form easily, so at most 0.4% or less is preferable. Should be kept below 0.2%.
  • Cr has the effect of increasing the strength by suppressing the formation of polygonal ferrite, so it can be added as necessary.
  • excessive addition may adversely affect the formation of the metal structure targeted by the present invention, so it should be suppressed to 1.0% or less at most.
  • delayed fracture resistance is also improved by controlling the ratio of the above elements within an appropriate range. Although the details of this reason are unknown, the following can be considered.
  • Mn promotes delayed fracture by reducing the grain boundary strength by segregation at the grain boundary, and also promotes the formation of voids that are the starting point of delayed fracture during processing through the formation of martensite as described above. Since A1 and A1 have the effect of increasing the allowable amount of hydrogen that induces delayed fracture, the delayed fracture property is considered to change depending on the ratio of the two.
  • the ratio of (Si + Al) / Mn (or Mn + Cr) is in the range of 0 ⁇ 74 to: 1.26, and more preferably 0. It should be adjusted to 84 or more and 1.16 or less.
  • Nb 0.1% or less
  • Ti 0.15% or less
  • Vanitic ferrite not only can easily achieve high strength at a certain degree of dislocation density, but also has the effect of reducing the hardness difference from the second phase and increasing stretch flangeability. It is also a useful structure for enhancing delayed fracture resistance. This structure has very little cementite, which is the starting point of delayed fracture, and very few dislocations. This is probably because of this. In order to exert these effects effectively, it is necessary to have 50% or more of the vitality tough light. More preferably, it is 60% or more.
  • this Vignite toughlite is clearly different from the bainitic structure in that it does not have carbides in the structure, and has a dislocation-free force or a polygome having an extremely small substructure. It is also different from the nal ferrite structure and the quasi-polygonal ferrite structure with substructures such as fine subgrains. These differences can be easily identified by TEM (transmission electron microscope) observation.
  • polygonal ferrite having an average grain size as described below is contained in a steel sheet of 980 MPa class or higher with a tensile strength of vinylic ferrite (BF) as the matrix, elongation is further improved.
  • BF vinylic ferrite
  • 5% or more of polygonal ferrite must be contained.
  • More preferable space factor of polygonal ferrite is 10% or more and 30% or less.
  • Average diameter of polygonal ferrite 10 ⁇ m or less
  • the average grain size of polygonal ferrite must be 10 ⁇ m or less. This is because by making the ferrite finer, the dispersion as the second phase is made uniform, the stretch flangeability and strength are both improved, and the delayed fracture resistance is also improved. This is thought to be because hydrogen is trapped at the ferrite grain boundaries, which increase as the polygonal ferrite is refined, and the concentration of hydrogen at the hazardous site is suppressed.
  • the average particle diameter of polygonal ferrite referred to here is the average value of the equivalent circle diameters of polygonal ferrite (the diameters of the circles having the same area). [0044] Residual ⁇ 5%
  • Residual ⁇ promotes hardening of the deformed part by transforming into martensite when the material is deformed due to strain, and has the effect of preventing strain concentration (TRIP effect).
  • TRIP effect strain concentration
  • There is no upper limit on the amount of residual flaws but a large amount of C is required to produce excessive residual ⁇ , making it difficult to achieve both spot weldability and workability, especially stretch flangeability. However, it is preferable to keep it below 30%.
  • martensite, bainite, pearlite, and the like may exist as the remaining structure other than the above, but these other structures do not adversely affect the above-described effects. It is desirable to keep it below 5%.
  • the production conditions for obtaining the above-described metal structure defined in the present invention are not particularly limited.
  • a general steel plate production procedure for example, continuous forging ⁇ hot rolling ⁇ pickling ⁇ cold rolling ⁇
  • the heating temperature, heating rate, holding temperature, cooling start temperature, cooling rate, etc. can be controlled appropriately.
  • it is only necessary to perform appropriate temperature control including the continuous hot-dip zinc plating line but the most important for obtaining the above metal structure is the heat treatment conditions in the continuous annealing line. An explanation will be given focusing on the preferred heat treatment conditions in the line.
  • Heating temperature during annealing Ac + 10 ° C or more
  • the heating temperature during annealing should be set to “Ac + 10 ° C. or higher”.
  • the heating temperature is “Ac + 30 ° C. or higher”.
  • the cooling rate after annealing is preferably faster because it suppresses the formation of polygonal ferrite, but considering the restrictions on equipment and the difficulty of temperature control, polygonal ferrite can be used depending on the individual component system. In order to keep it below a certain amount, preferably 25 ° CZsec or more, more preferably Preferably, it should be 30 ° C / sec or higher.
  • the temperature at which rapid cooling after annealing should be stopped should be below the temperature at which fine polygonal ferrite is formed, preferably below 650 ° C, more preferably below 600 ° C. If the quenching stop temperature increases, polygonal ferrite becomes coarse, and the object of the present invention cannot be achieved. However, since a sufficient amount of polygonal ferrite cannot be obtained when the temperature is too low, it should be about 360 ° C or higher, more preferably 400 ° C.
  • a preferable holding temperature for obtaining the metal structure of the present invention is in the range of 360 to 440 ° C.
  • the preferred holding time is 1 minute or longer.
  • the holding temperature needs to be lower than the rapid cooling stop temperature. As a result, after passing through a temperature range where fine ferrite is likely to be generated, it is brought to the vinegar toughness transformation temperature range.
  • the high-strength composite steel sheet according to the present invention uses a steel material having a specified chemical component as described above, and adopts appropriate heat treatment conditions including cooling conditions, holding conditions, etc. By securing the structure, it is possible to provide a low-cost composite steel sheet having high strength of 980 MPa or higher, good formability, and excellent spot weldability and delayed fracture resistance.
  • Heating temperature 1200 ° C x 60 minutes
  • Cooling Cooled to 720 ° C at 40 ° C / second, air-cooled for 10 seconds, then cooled to 500 ° C at 40 ° C / second, held at 500 ° C for 60 minutes, and then cooled in the furnace.
  • the metal structure of the obtained cold-rolled steel sheet was confirmed by the following method, and each test steel sheet was subjected to a tensile test, a hole expansion test, a spot welding test, and a delayed fracture resistance test. And obtained the result.
  • PF can be distinguished from residual ⁇ and martensite white because it corrodes gray.
  • the circumference of polygonal ferrite in the SEM photograph by the above ⁇ was traced, and the equivalent circle diameter was calculated from the trace image by image analysis.
  • the average value of the equivalent circle diameter was defined as the average particle diameter of polygonal ferrite.
  • Vinety Tough Light (BF): With a transmission electron microscope (TEM: magnification of 15000), it was confirmed that the structure was not other structures such as bainite and pseudofluorite. Martensite ( ⁇ ) and bainite ( ⁇ ) were reduced.
  • Tensile test Measured with a JIS No. 5 tensile test piece.
  • Experiments Nos. 1 to 10 and 16 are examples that satisfy all of the specified requirements of the present invention, and all have tensile strength of 98 OMPa class or higher, strength X elongation characteristics, strength X elongation flange characteristics The formability evaluated by the properties is good, and even if spot weldability is poor in delayed fracture resistance, good results can be obtained.
  • Experiment No. 11 was evaluated based on strength X elongation characteristics and strength X elongation flange characteristics because the C content of the steel material was insufficient and the amount of vanitic ferrite in the metal structure was also insufficient. The moldability is also poor.
  • the experiment No. 12 since the Si content of the steel used is out of the (Si + Al) / (Mn + Cr) ratio specified range as well as lack, there is no residual ⁇ in the metal structure, strength X Elongation characteristics and strength The formability evaluated by the X-stretch flange characteristics is inferior and delayed fracture resistance is poor.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne une feuille d'acier composite à résistance élevée dotée d'une résistance à la traction de 980 MPa ou plus et dont l'aptitude au moulage, la résistance à la rupture différée et la soudabilité par points sont excellentes. La feuille d'acier comprend un acier dont la composition chimique est la suivante : C : de 0,12 à 0,25 %, Si : de 1,0 à 3,0 %, Mn : de 1,5 à 3,0 %, P : 0,15 % ou moins, S : 0,02 % ou moins, Al : 0,4 % ou moins, et Cr : 1,0 % ou moins, le complément étant du fer et des impuretés inévitables, dans laquelle les teneurs en Si, Al, Mn et Cr satisfont la relation exprimée par la formule suivante : (Si+Al)/Mn ou (Si+Al)/(Mn+Cr) = 0,74 à 1,26 ; la feuille d'acier a une microstructure déterminée.
PCT/JP2007/061301 2006-06-05 2007-06-04 Feuille d'acier composite à résistance élevée dotée d'excellentes aptitude au moulage et résistance à la fracture différée Ceased WO2007142197A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
GB0900057.1A GB2452230B (en) 2006-06-05 2007-06-04 High-strength composite steel sheet having excellent formability and anti-delayed fraction property
CN2007800208296A CN101460646B (zh) 2006-06-05 2007-06-04 成形性、耐延迟破坏性优异的高强度复合组织钢板
US12/303,566 US20100221138A1 (en) 2006-06-05 2007-06-04 High-strength composite steel sheet having excellent moldability and delayed fracture resistance

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2006156442A JP4974341B2 (ja) 2006-06-05 2006-06-05 成形性、スポット溶接性、および耐遅れ破壊性に優れた高強度複合組織鋼板
JP2006-156442 2006-06-05

Publications (1)

Publication Number Publication Date
WO2007142197A1 true WO2007142197A1 (fr) 2007-12-13

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PCT/JP2007/061301 Ceased WO2007142197A1 (fr) 2006-06-05 2007-06-04 Feuille d'acier composite à résistance élevée dotée d'excellentes aptitude au moulage et résistance à la fracture différée

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US (1) US20100221138A1 (fr)
JP (1) JP4974341B2 (fr)
KR (1) KR20090016500A (fr)
CN (1) CN101460646B (fr)
GB (1) GB2452230B (fr)
WO (1) WO2007142197A1 (fr)

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JP2010255097A (ja) * 2009-02-25 2010-11-11 Jfe Steel Corp 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
WO2012118040A1 (fr) * 2011-03-02 2012-09-07 株式会社神戸製鋼所 Tôle d'acier à haute résistance présentant une excellente aptitude à l'emboutissage profond à température ambiante et à des températures chaudes et procédé pour le travail à chaud de celle-ci
WO2014092025A1 (fr) * 2012-12-12 2014-06-19 株式会社神戸製鋼所 Plaque d'acier à résistance élevée et son procédé de fabrication
WO2017108866A1 (fr) * 2015-12-21 2017-06-29 Arcelormittal Procédé pour la production d'une tôle d'acier à haute résistance ayant une ductilité et une aptitude au formage améliorées et tôle d'acier ainsi obtenue
RU2680042C2 (ru) * 2014-07-03 2019-02-14 Арселормиттал Способ производства высокопрочного стального листа, обладающего улучшенной прочностью, пластичностью и формуемостью
US12084738B2 (en) 2015-12-21 2024-09-10 Arcelormittal Method for producing a steel sheet having improved strength, ductility and formability

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JP5883211B2 (ja) * 2010-01-29 2016-03-09 株式会社神戸製鋼所 加工性に優れた高強度冷延鋼板およびその製造方法
JP5671359B2 (ja) 2010-03-24 2015-02-18 株式会社神戸製鋼所 温間加工性に優れた高強度鋼板
JP5662902B2 (ja) 2010-11-18 2015-02-04 株式会社神戸製鋼所 成形性に優れた高強度鋼板、温間加工方法、および温間加工された自動車部品
WO2012133057A1 (fr) 2011-03-31 2012-10-04 株式会社神戸製鋼所 Tôle d'acier à haute résistance présentant une excellente aptitude au façonnage, et son procédé de fabrication
US9745639B2 (en) 2011-06-13 2017-08-29 Kobe Steel, Ltd. High-strength steel sheet excellent in workability and cold brittleness resistance, and manufacturing method thereof
JP5636347B2 (ja) 2011-08-17 2014-12-03 株式会社神戸製鋼所 室温および温間での成形性に優れた高強度鋼板およびその温間成形方法
JP5860308B2 (ja) * 2012-02-29 2016-02-16 株式会社神戸製鋼所 温間成形性に優れた高強度鋼板およびその製造方法
JP5632904B2 (ja) 2012-03-29 2014-11-26 株式会社神戸製鋼所 加工性に優れた高強度冷延鋼板の製造方法
US10106874B2 (en) 2012-03-30 2018-10-23 Voestalpine Stahl Gmbh High strength cold rolled steel sheet
EP2831299B2 (fr) 2012-03-30 2020-04-29 Voestalpine Stahl GmbH Tôle d'acier laminée à froid à haute résistance et procédé de production d'une tôle d'acier de ce type
PL2684975T3 (pl) * 2012-07-10 2017-08-31 Thyssenkrupp Steel Europe Ag Produkt stalowy płaski, walcowany na zimno i sposób jego wytwarzania
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JP5821912B2 (ja) * 2013-08-09 2015-11-24 Ｊｆｅスチール株式会社 高強度冷延鋼板およびその製造方法
JP5728115B1 (ja) 2013-09-27 2015-06-03 株式会社神戸製鋼所 延性および低温靭性に優れた高強度鋼板、並びにその製造方法
WO2016001710A1 (fr) 2014-07-03 2016-01-07 Arcelormittal Procédé de fabrication d'un acier revêtu à haute résistance ayant une résistance et une ductilité améliorée et tôle obtenue
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CN111757946B (zh) * 2018-03-30 2022-04-05 日本制铁株式会社 钢板
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WO2017108866A1 (fr) * 2015-12-21 2017-06-29 Arcelormittal Procédé pour la production d'une tôle d'acier à haute résistance ayant une ductilité et une aptitude au formage améliorées et tôle d'acier ainsi obtenue
WO2017109540A1 (fr) * 2015-12-21 2017-06-29 Arcelormittal Procédé de fabrication d'une tôle d'acier à haute résistance ayant une ductilité et une aptitude au formage améliorées et tôle d'acier ainsi obtenue
EP3656880A1 (fr) * 2015-12-21 2020-05-27 ArcelorMittal Procédé pour la production d'une tôle d'acier à haute résistance ayant une ductilité et une aptitude au formage améliorées et tôle d'acier ainsi obtenue
EP3910084A1 (fr) * 2015-12-21 2021-11-17 ArcelorMittal Procédé pour la production d'une tôle d'acier à haute résistance ayant une ductilité et une aptitude au formage améliorées et tôle d'acier ainsi obtenue
US12054799B2 (en) 2015-12-21 2024-08-06 Arcelormittal Method for producing a high strength steel sheet having improved ductility and formability, and obtained steel sheet
US12084738B2 (en) 2015-12-21 2024-09-10 Arcelormittal Method for producing a steel sheet having improved strength, ductility and formability

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