EP2987887B1 - Tôle d'acier à haute résistance mécanique laminée à chaud et son procédé de production - Google Patents

Tôle d'acier à haute résistance mécanique laminée à chaud et son procédé de production Download PDF

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EP2987887B1
EP2987887B1 EP14785555.5A EP14785555A EP2987887B1 EP 2987887 B1 EP2987887 B1 EP 2987887B1 EP 14785555 A EP14785555 A EP 14785555A EP 2987887 B1 EP2987887 B1 EP 2987887B1
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less
phase
hot rolled
rolled steel
steel sheet
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German (de)
English (en)
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EP2987887A4 (fr
EP2987887A1 (fr
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Kazuhiko Yamazaki
Katsumi Nakajima
Chikara Kami
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JFE Steel Corp
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JFE Steel Corp
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Priority claimed from JP2013084448A external-priority patent/JP5867444B2/ja
Priority claimed from JP2013084450A external-priority patent/JP5870955B2/ja
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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • C21D8/04—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
    • C21D8/0426—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
    • C21D8/04—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
    • C21D8/0447—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 heat treatment
    • C21D8/0463—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 heat treatment following 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/003—Cementite
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to a high strength hot rolled steel sheet having a tensile strength of 980 MPa or more, which is suitable for a material for structural parts and frameworks of automobiles, frames of trucks, steel pipes, and the like.
  • the high strength hot rolled steel sheet having tensile strength: 980 MPa or more is highly expected to serve as a material capable of improving fuel efficiency of automobile by leaps and bounds or a material capable of reducing the construction cost of pipeline to a large extent.
  • Patent Literature 1 proposes a hot rolled steel sheet with sheet thickness: 4.0 mm or more and 12 mm or less, having a composition containing, on a percent by mass basis, C: 0.04% to 0.12%, Si: 0.5% to 1.2%, Mn: 1.0% to 1.8%, P: 0.03% or less, S: 0.0030% or less, Al: 0.005% to 0.20%, N: 0.005% or less, Ti: 0.03% to 0.13%, and the balance being Fe and incidental impurities and a microstructure in which the area fraction of bainite phase is more than 95% and the average grain size of the bainite phase is 3 ⁇ m or less, wherein a difference between the Vickers hardness at the position at 50 ⁇ m from the surface layer and the Vickers hardness at the position one-quarter of the sheet thickness is specified to be 50 or less, and a difference between the Vickers hardness at the position one-quarter of the sheet thickness and the Vickers hardness at the position at one-half of the sheet thickness is specified
  • Patent Literature 1 a high strength hot rolled steel sheet exhibiting excellent toughness and having tensile stress: 780 MPa or more is obtained by specifying the principal phase to be fine bainite and reducing the hardness distribution in the sheet thickness direction.
  • Patent Literature 2 proposes a method for manufacturing a steel sheet, including the steps of heating a steel material satisfying, on a percent by mass basis, C: 0.05% to 0.18%, Si: 0.10% to 0.60%, Mn: 0.90% to 2.0%, P: 0.025% or less (excluding 0%), S: 0.015% or less (excluding 0%), Al: 0.001% to 0.1%, and N: 0.002% to 0.01%, and the balance being Fe and incidental impurities, to 950°C or higher and 1,250°C or lower, starting rolling, completing the rolling at 820°C or higher, performing cooling to 600°C to 700°C at a cooling rate of 20°C/s or more, performing holding at that temperature range for 10 to 200 seconds or performing slow cooling and, thereafter, performing cooling to 300°C or lower at a cooling rate of 5°C/s or more, wherein the metal microstructure is specified to be ferrite: 70% to 90%, martensite or a mixed phase of martensite and austenite: 3% to
  • Patent Literature 2 a high toughness steel sheet which has a tensile strength of 490 N/mm 2 or more and which exhibits a low yield ratio, where the yield ratio is 70% or less, is obtained by specifying the metal microstructure to be a microstructure including ferrite having fine crystal grains, martensite or a mixed phase of martensite and austenite, and the like.
  • Patent Literature 3 proposes a method for manufacturing a thick high strength hot rolled steel sheet, including the steps of subjecting a steel material containing, on a percent by mass basis, C: 0.02% to 0.25%, Si: 1.0% or less, Mn: 0.3% to 2.3%, P: 0.03% or less, S: 0.03% or less, Al: 0.1% or less, Nb: 0.03% to 0.25%, and Ti: 0.001% to 0.10%, where (Ti + Nb/2)/C ⁇ 4 is satisfied, to hot rolling, applying first cooling after finish rolling of the hot rolling is completed, where accelerated cooling is performed at an average cooling rate of hot-rolled sheet surface of 20°C/s or more and less than martensite formation critical cooling rate until the surface temperature reaches the Ar 3 transformation temperature or lower and the Ms temperature or lower, applying second cooling, where quenching is performed until the sheet thickness center temperature reaches 350°C or higher and lower than 600°C, performing coiling into the shape of a coil at a coiling temperature of 350°C
  • Patent Literature 3 a material for X65 grade or higher of high strength electric resistance welded steel pipe exhibiting excellent low-temperature toughness is obtained by specifying the microstructure of the hot rolled steel sheet to be a bainite phase or bainitic ferrite phase and, furthermore, adjusting the amount of grain boundary cementite to a specific value or less.
  • Patent Literature 4 A further high-strength hot rolled steel sheet having excellent toughness and a method for producing the same is disclosed in Patent Literature 4.
  • Patent Literature 1 the high strength hot rolled steel sheet having tensile strength: 980 MPa or more is obtained.
  • the control of the bainite microstructure is insufficient and, thereby, there is a problem that excellent low-temperature toughness cannot be obtained stably.
  • the metal microstructure of the steel is specified to be the structure including a ferrite phase as a primary phase, although in the case where the tensile strength is in the 980 MPa class, the toughness of the ferrite phase may be degraded significantly.
  • the present invention solves the above-described problems included in the technologies of the related art advantageously, and it is an object to provide a high strength hot rolled steel sheet having high strength of tensile strength: 980 MPa or more, further exhibiting good toughness and, in particular, having a sheet thickness of 4 mm or more and 15 mm or less and a method for manufacturing the same.
  • the present inventors conducted intensive research to improve the toughness of a hot rolled steel sheet while the high strength of tensile strength TS: 980 MPa or more had.
  • the bainite phase was noted, where it is known that the bainite phase has good strength-toughness balance in general, and various factors affecting the strength and the toughness of the hot rolled steel sheet, in which the primary phase of the microstructure was bainite, were studied. As a result, it was found that allowing laths of the bainite phase to become fine was very effective in enhancing strength and improving toughness of the hot rolled steel sheet. Then, further studies were conducted.
  • a high strength hot rolled steel sheet having a tensile strength of 980 MPa or more and exhibiting excellent toughness is obtained. Therefore, the car body weight can be reduced while the safety of the automobile is ensured and an environmental load can be reduced by applying the present invention to structural parts and frameworks of automobiles, frames of trucks, and the like.
  • a welded steel pipe produced from the hot rolled steel sheet according to the present invention serving as a material instead of the UOE pipe produced from a steel plate serving as a material is applied to a transport pipe, the productivity is improved and the cost can be further reduced.
  • the present invention can stably produce a hot rolled steel sheet exhibiting improved toughness while high strength of tensile strength: 980 MPa or more has and, therefore, is very useful for the industry.
  • the C content is 0.10% or more.
  • the C content is specified to be more than 0.10% and 0.16% or less.
  • the amount of Mn is 2.5% or more and 3.5% or less
  • the amount of C is preferably 0.06% or more and 0.15% or less.
  • Si is an element which suppresses coarse oxides and cementite to impair the toughness and which contributes to solute strengthening. If the content is more than 1.0%, the surface quality of the hot rolled steel sheet is degraded significantly and degradation in the chemical conversion treatability and the corrosion resistance is caused. Therefore, the Si content is specified to be 1.0% or less, and preferably 0.4% or more and 0.8% or less.
  • Mn is an element which contributes to enhancement of strength of the steel through solid solution and which facilitates formation of bainite through improvement of the hardenability. In order to obtain such effects, it is necessary that the Mn content be 1.8% or more. On the other hand, if the Mn content is more than 3.5%, center segregation becomes considerable, and the toughness of the hot rolled steel sheet is degraded. Therefore, the Mn content is specified to be 1.8% or more and 3.5% or less. In this regard, 1.8% or more and 2.5% or less is preferable.
  • P is an element which contributes to enhancement of strength of the steel through solid solution but is an element which segregates at grain boundaries, in particular prior-austenite grain boundaries, to cause degradation in low-temperature toughness and workability. Consequently, it is preferable that the P content be minimized, although the content up to 0.04% is allowable. Therefore, the P content is specified to be 0.04% or less. However, when the P content is excessively reduced, an effect corresponding to an increase in the smelting cost is not obtained, so that the P content is specified to be preferably 0.003% or more and 0.03% or less, and more preferably 0.005% or more and 0.02% or less.
  • the S content is specified to be 0.006% or less.
  • the S content is specified to be preferably 0.0003% or more and 0.004% or less, and more preferably 0.0005% or more and 0.002% or less.
  • A1 is an element which functions as a deoxidizing agent and which is effective in improving cleanliness of the steel.
  • excessive addition of Al causes increases in oxide inclusions, degrades the toughness of the hot rolled steel sheet and, in addition, causes an occurrence of flaw. Therefore, the Al content is specified to be 0.10% or less, preferably 0.005% or more and 0.08% or less, and further preferably 0.01% or more and 0.05% or less.
  • N bonds to Ti at a high temperature to form coarse nitrides easily and degrades the toughness of the hot rolled steel sheet. Consequently, the N content is specified to be 0.008% or less, preferably 0.001% or more and 0.006% or less, and more preferably 0.002% or more and 0.005% or less.
  • Ti is one of the most important elements in the present invention. Ti contributes to enhancement of strength of the steel through formation of carbonitrides to make crystal grains fine and through precipitation strengthening. Also, Ti forms many fine (Ti,V)C clusters at low temperatures of 300°C or higher and 450°C or lower, reduces the amount of cementite in the steel, and improve the toughness of the hot rolled steel sheet. In order to exert such effects, it is necessary that the Ti content be 0.05% or more. On the other hand, if the Ti content is excessive and is more than 0.20%, the above-described effects are saturated, an increase in coarse precipitates is caused, and degradation in the toughness of the hot rolled steel sheet is caused. Therefore, the Ti content is limited to within the range of 0.05% or more and 0.20% or less, and preferably 0.08% or more and 0.15% or less.
  • V more than 0.1% and 0.3% or less
  • V is one of the most important elements in the present invention.
  • V contributes to enhancement of strength of the steel through formation of carbonitrides to make crystal grains fine and through precipitation strengthening. Also, V improves the hardenability and contributes to formation and making fine of bainite phase.
  • V forms many fine (Ti,V)C clusters at low temperatures of 300°C or higher and 450°C or lower, reduces the amount of cementite in the steel, and improves the toughness of the hot rolled steel sheet. In order to exert such effects, it is necessary that the V content be more than 0.1%. On the other hand, if the V content is excessive and is more than 0.3%, the above-described effects are saturated, so that the cost increases. Therefore, the V content is limited to within the range of more than 0.1% and 0.3% or less, and preferably 0.15% or more and 0.25% or less.
  • the basic components of the hot rolled steel sheet according to the present invention are as described above.
  • the hot rolled steel sheet according to the present invention may further contain, as necessary, at least one selected from Nb: 0.005% or more and 0.4% or less, B: 0.0002% or more and 0.0020% or less, Cu: 0.005% or more and 0.2% or less, Ni: 0.005% or more and 0.2% or less, Cr: 0.005% or more and 0.4% or less, and Mo: 0.005% or more and 0.4% or less for the purpose of, for example, improvement of toughness and enhancement of strength.
  • Nb 0.005% or more and 0.4% or less
  • Nb is an element which contributes to enhancement of strength of the steel through formation of carbonitrides. In order to exert such an effect, it is preferable that the Nb content be 0.005% or more. On the other hand, if the Nb content is more than 0.4%, deformation resistance increases, so that a rolling force of hot rolling increases in production of the hot rolled steel sheet, a load to a rolling mill becomes too large, and rolling operation in itself may become difficult. Meanwhile, if the Nb content is more than 0.4%, coarse precipitates are formed and the toughness of the hot rolled steel sheet tends to be degraded. Therefore, the Nb content is preferably specified to be 0.005% or more and 0.4% or less. In this regard, 0.01% or more and 0.3% or less is more preferable and 0.02% or more and 0.2% or less is further preferable.
  • B is an element which segregates at austenite grain boundaries and which suppresses formation and growth of ferrite. Also, B is an element which improves the hardenability and which contributes to formation and making fine of bainite phase. In order to exert these effects, it is preferable that the B content be 0.0002% or more. However, if the B content is more than 0.0020%, formation of martensite phase is facilitated, so that the toughness of the hot rolled steel sheet may be degraded significantly. Therefore, in the case where B is contained, the content thereof is specified to be preferably 0.0002% or more and 0.0020% or less. In this regard, 0.0004% or more and 0.0012% or less is more preferable.
  • Cu is an element which contributes to enhancement of strength of the steel through solid solution. Also, Cu is an element which has a function of improving hardenability, which lowers, in particular, the bainite transformation temperature, and which contributes to making bainite phase fine. In order to obtain these effects, it is preferable that the Cu content be 0.005% or more, although if the content thereof is more than 0.2%, degradation in the surface quality of the hot rolled steel sheet is caused. Therefore, the Cu content is specified to be preferably 0.005% or more and 0.2% or less. In this regard, 0.01% or more and 0.15% or less is more preferable.
  • Ni 0.005% or more and 0.2% or less
  • Ni is an element which contributes to enhancement of strength of the steel through solid solution. Also, Ni has a function of improving hardenability and facilitates formation of bainite phase. In order to obtain these effects, it is preferable that the Ni content be 0.005% or more. However, if the Ni content is more than 0.2%, a martensite phase is generated easily, and the toughness of the hot rolled steel sheet may be degraded significantly. Therefore, the Ni content is specified to be preferably 0.005% or more and 0.2% or less, and more preferably 0.01% or more and 0.15% or less.
  • the Cr forms carbides and contributes to enhancement of strength of the hot rolled steel sheet.
  • the Cr content be 0.005% or more.
  • the Cr content is specified to be preferably 0.005% or more and 0.4% or less, and more preferably 0.01% or more and 0.2% or less.
  • Mo facilitates formation of bainite phase through improvement of the hardenability and contributes to improvement of the toughness and enhancement of strength of the hot rolled steel sheet.
  • the Mo content be 0.005% or more.
  • the Mo content is specified to be preferably 0.005% or more and 0.4% or less, and more preferably 0.01% or more and 0.2% or less.
  • the hot rolled steel sheet according to the present invention may contain, as necessary, one or two selected from Ca: 0.0002% or more and 0.01% or less and REM: 0.0002% or more and 0.01% or less.
  • the Ca is effective in controlling the shape of sulfide inclusions and improving bending workability and the toughness of the hot rolled steel sheet.
  • the Ca content be 0.0002% or more.
  • the Ca content is specified to be preferably 0.0002% or more and 0.01% or less. In this regard, 0.0004% or more and 0.005% or less is more preferable.
  • REM controls the shape of sulfide inclusions and improves adverse influences of sulfide inclusions on the bending workability and the toughness of the hot rolled steel sheet.
  • the REM content be 0.0002% or more.
  • the content thereof is specified to be preferably 0.0002% or more and 0.01% or less. In this regard, 0.0004% or more and 0.005% or less is more preferable.
  • the remainder other than those described above is composed of Fe and incidental impurities.
  • incidental impurities include Sb, Sn, and Zn.
  • Sb 0.01% or less
  • Sn 0.1% or less
  • Zn 0.01% or less are allowable.
  • the hot rolled steel sheet according to the present invention has a microstructure in which a primary phase is more than 85% on an area fraction basis of bainite phase, a secondary phase is at least one of ferrite phase, martensite phase, and retained austenite phase, 0% or more and less than 15% in total on an area fraction basis of secondary phase is contained, the average lath interval of laths of the above-described bainite phase is 400 nm or less, and the average long axis length of the above-described laths is 5.0 ⁇ m or less.
  • the primary phase of the hot rolled steel sheet according to the present invention is a bainite phase having excellent strength-toughness balance. If the fraction of the bainite phase is 85% or less on an area fraction basis, a hot rolled steel sheet provided with predetermined strength and toughness is not obtained. Therefore, the fraction of the bainite phase is specified to be more than 85% on an area fraction basis, preferably 87% or more, and more preferably 90% or more. It is still more preferable that the fraction of the bainite phase be 100% on an area fraction basis and the microstructure be a bainite single phase microstructure.
  • the hot rolled steel sheet according to the present invention includes a secondary phase, which is composed of at least one of ferrite phase, martensite phase, and retained austenite phase, as a microstructure other than the bainite phase serving as the primary phase.
  • the microstructure is specified to be preferably a bainite single phase microstructure to impart predetermined strength and toughness to the hot rolled steel sheet.
  • the fraction of the above-described secondary phase in total is specified to be 0% or more and less than 15% on an area fraction basis, preferably 13% or less, and more preferably 11% or less.
  • Average lath interval of laths of bainite phase 400 nm or less
  • Average long axis length of laths of bainite phase 5.0 ⁇ m or less
  • the average lath interval of laths of the bainite phase is specified to be 400 nm or less, and preferably 350 nm or less.
  • the average long axis length of laths of the bainite phase is specified to be 5.0 ⁇ m or less, and preferably 4.0 ⁇ m or less.
  • lower limits of the average lath interval of laths of the bainite and the average long axis length of laths of the bainite phase are not particularly specified.
  • the lath interval and the long axis length are determined on the basis of the bainite transformation temperature and, therefore, usually the average lath interval of laths of the bainite phase is 100 nm or more and the average long axis length of laths of the bainite phase is 1.0 ⁇ m or more.
  • a high strength hot rolled steel sheet having a tensile strength of 980 MPa or more and having toughness required of a material for structural parts of automobiles and a material for steel pipes, e.g., line pipes, is obtained by specifying the composition and the microstructure, as described above.
  • the sheet thickness of the hot rolled steel sheet according to the present invention is not specifically limited, although the sheet thickness is specified to be preferably about 4 mm or more and 15 mm or less.
  • the present invention is characterized by heating a steel having the above-described composition to 1,200°C or higher, applying hot rolling composed of rough rolling and finish rolling in which the accumulated rolling reduction is 50% or more in a temperature range of 1,000°C or lower and the finishing temperature is 820°C or higher and 930°C or lower, starting cooling within 4.0 s of the hot rolling, performing cooling at an average cooling rate of 20°C/s or more, and performing coiling at a coiling temperature of 300°C or higher and 450°C or lower.
  • the method for manufacturing a steel is not necessarily particularly limited, and any common method can be applied, wherein a molten steel having the above-described composition is refined in a converter or the like, and a steel, e.g., a slab, is produced by a casting method, e.g., a continuous casting method.
  • a casting method e.g., a continuous casting method.
  • an ingot-making and blooming method may be used.
  • electro-magnetic stirrer EMS
  • IBSR intentional bulging soft reduction casting
  • Equiaxial crystals are formed in the sheet thickness center portion by applying an electro-magnetic stirrer treatment, so that segregation can be reduced.
  • segregation in the sheet thickness center portion can be reduced by preventing flowing of the molten steel in an unsolidified portion of the continuous casting slab.
  • the toughness described below can be brought to a more excellent level by applying at least one of these segregation reduction treatments.
  • Heating temperature of steel 1,200°C or higher
  • the heating temperature of the steel is specified to be preferably 1,350°C or lower, and more preferably 1,220°C or higher and 1,300°C or lower.
  • the steel material is heated to the heating temperature of 1, 200°C or higher and is held for a predetermined time. If the holding time is more than 4,800 seconds, the amount of generation of scale increases and, as a result, scale biting and the like occurs easily in the following hot rolling step, and the surface quality of the hot rolled steel sheet tends to be degraded. Therefore, the holding time of the steel material in the temperature range of 1,200°C or higher is specified to be preferably 4,800 seconds or less, and more preferably 4,000 seconds or less.
  • the steel material is subjected to hot rolling having rough rolling and finish rolling.
  • the condition of the rough rolling is not specifically limited insofar as predetermined sheet bar dimensions are ensured.
  • the finish rolling is applied. In this regard, preferably, descaling is performed before the finish rolling or between stands during rolling.
  • the accumulated rolling reduction is specified to be 50% or more in a temperature range of 1,000°C or lower and the finishing temperature is specified to be 820°C or higher and 930°C or lower.
  • the rolling reduction in a relatively low temperature range be increased and crystal grains after rolling be allowed to become crystal grains elongated in the rolling direction (crystal grains having a high elongation rate). If the accumulated rolling reduction at 1,000°C or lower is less than 50%, it becomes difficult to make bainite having a predetermined lath structure (average lath interval: 400 nm or less, average long axis length: 5.0 ⁇ m or less), and the toughness of the hot rolled steel sheet is degraded. Therefore, the accumulated rolling reduction at 1,000°C or lower is specified to be 50% or more, and preferably 60% or more.
  • the accumulated rolling reduction in a temperature range of 1,000°C or lower is excessively high, crystal grains are excessively elongated in the rolling direction and ferrite is generated easily, so that it may also be difficult to make bainite having a predetermined lath structure. Consequently, the accumulated rolling reduction in a temperature range of 1,000°C or lower is specified to be preferably 80% or less.
  • Finishing temperature 820°C or higher and 930°C or lower If the finishing temperature of the finishing rolling is lower than 820°C, rolling is performed at a temperature of two-phase region of ferrite + austenite, so that a deformation microstructure remains after rolling and the toughness of the hot rolled steel sheet is degraded. On the other hand, if the finishing temperature is higher than 930°C, austenite grains grow, and a bainite phase of the hot rolled steel sheet obtained after cooling is coarsened. As a result, it becomes difficult to make a predetermined microstructure, and the toughness of the hot rolled steel sheet is degraded. Therefore, the finishing temperature is specified to be 820°C or higher and 930°C or lower, and preferably 840°C or higher and 920°C or lower. Here, the finishing temperature refers to the surface temperature of a sheet.
  • Forced cooling is started within 4.0 s of, preferably just after, completion of the finish rolling, cooling is stopped at the coiling temperature, and coiling into the shape of a coil is performed. If the time from completion of the finish rolling to start of the forced cooling is more than 4.0 s and is long, austenite grains become coarse, and a bainite phase is coarsened. Also, austenite grains become coarse, so that the hardenability of the steel sheet increases and a martensite phase is generated easily. In the case where the bainite phase is coarsened and the martensite phase is generated easily, predetermined excellent toughness cannot be obtained. Therefore, the forced cooling start time is limited to within 4.0 s of completion of the finish rolling.
  • Average cooling rate 20°C/s or more
  • the above-described average cooling rate is specified to be 20°C/s or more, and preferably 30°C/s or more.
  • the upper limit of the average cooling rate is not particularly specified.
  • the average cooling rate is specified to be preferably 60°C/s or less.
  • the above-described average cooling rate is specified to be an average cooling rate of the steel sheet surface.
  • Coiling temperature 300°C or higher and 450°C or lower
  • the coiling temperature is specified to be within the range of 300°C or higher and 450°C or lower, and preferably 330°C or higher and 430°C or lower.
  • the hot rolled steel sheet may be subjected to temper rolling following the common method or be subjected to pickling to remove scale formed on the surface.
  • a galvanization process e.g., hot dip galvanizing or electrogalvanizing, and a chemical conversion treatment may further be applied.
  • a molten steel having the composition shown in Table 1 was refined in a converter, and a slab (steel) was produced by a continuous casting method.
  • those other than Hot rolled steel sheet No. 1' of Steel Al in Tables 1 to 3 described below were subjected to electro-magnetic stirrer (EMS) for the purpose of segregation reduction treatment of the components.
  • EMS electro-magnetic stirrer
  • these steel materials were heated under the conditions shown in Table 2, and were subjected to hot rolling having rough rolling and finish rolling under the conditions shown in Table 2.
  • cooling was performed under the conditions shown in Table 2, and coiling was performed at coiling temperatures shown in Table 2, so that hot rolled steel sheets having sheet thicknesses shown in Table 2 were produced.
  • Test pieces were taken from the resulting hot rolled steel sheets, and microstructure observation, a tensile test, and a Charpy impact test were performed.
  • the microstructure observation method and various testing methods were as described below.
  • a test piece for a scanning electron microscope (SEM) was taken from the hot rolled steel sheet, a sheet thickness cross-section parallel to the rolling direction was polished and, thereafter, the microstructure was allowed to appear with a corrosive liquid (3% nital solution). Photographs were taken in three fields of view of each of the position at one-quarter of the sheet thickness and the position at one-half of the sheet thickness (center position of the sheet thickness) with a scanning electron microscope (SEM) at the magnification of 3,000 times, and the area fraction of each phase was quantified on the basis of an image treatment.
  • SEM scanning electron microscope
  • a test piece having size: 10 mm ⁇ 15 mm was taken from the hot rolled steel sheet, thin film samples for transmission electron microscope (TEM) observation of the position at one-quarter of the sheet thickness and the position at one-half of the sheet thickness (center position of the sheet thickness) were produced, and photographs were taken in ten fields of view of each position with TEM at the magnification of 30,000 times.
  • Five straight lines at intervals of 10 mm were drawn at right angles to long axes of at least three laths which were shown in each photograph having a size of 120 mm ⁇ 80 mm and which were successively arranged side by side.
  • the length of each line segment between the intersection points of the straight line and the lath boundary was measured and the average value of the resulting lengths of the segments was specified to be the average lath interval.
  • a test piece for a scanning electron microscope (SEM) was taken from the hot rolled steel sheet, a sheet thickness cross-section parallel to the rolling direction was polished and, thereafter, the microstructure was allowed to appear with a corrosive liquid (3% nital solution). Photographs were taken in five fields of view of each of the position at one-quarter of the sheet thickness and the position at one-half of the sheet thickness (center position of the sheet thickness) with a scanning electron microscope (SEM) at the magnification of 10,000 times.
  • SEM scanning electron microscope
  • JIS No. 5 test pieces (GL: 50 mm) were taken from the hot rolled steel sheet in such a way that the tensile direction and the rolling direction form a right angle.
  • a tensile test was performed in conformity with JIS Z 2241 (2011) and the yield strength (yield point) YP, the tensile strength (TS), and the total elongation El were determined.
  • a subsize test piece (V-notch) having a thickness of 5 mm was taken from the hot rolled steel sheet in such a way that the longitudinal direction of the test piece and the rolling direction form a right angle.
  • a Charpy impact test was performed in conformity with JIS Z 2242, the Charpy impact value (vE- 50 ) at a temperature of -50°C was measured, and the toughness was evaluated.
  • the hot rolled steel sheet having a sheet thickness of more than 5 mm was subjected to double-side polishing to produce a test piece having a sheet thickness of 5 mm.
  • a test piece having the original sheet thickness was produced. Then, the test pieces were subjected to the charpy impact test. In the case where the measured vE -50 value was 40 J or more, the toughness was evaluated as good.
  • the hot rolled steel sheets of Invention examples are hot rolled steel sheets having predetermined strength (TS: 980 MPa or more) and excellent toughness (vE -50 value: 40 J or more) in combination. Also, the hot rolled steel sheets of Invention examples have predetermined strength and excellent toughness at each of the position at 1/4 of sheet thickness and the position at 1/2 of sheet thickness (sheet thickness center position) and, therefore, are hot rolled steel sheets having good characteristics in the entire region in the sheet thickness direction. On the other hand, the hot rolled steel sheets of Comparative examples out of the scope of the present invention are unable to obtained predetermined strength or are unable to obtained sufficient toughness.

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Claims (2)

  1. Tôle d'acier laminée à chaud hautement résistante ayant résistance à la traction TS de 980 MPa ou plus, comprenant une composition et une microstructure,
    la composition étant constituée, sur une base de pourcentage en masse, de
    C : plus de 0,10 % et 0,16 % ou moins, Si : 1,0 % ou moins, Mn : 1,8 % ou plus et 3,5 % ou moins, P : 0,04 % ou moins, S : 0,006 % ou moins, Al : 0,10 % ou moins, N : 0,008 % ou moins, Ti : 0,05 % ou plus et 0,20 % ou moins, V : plus de 0,1 % et 0,3 % ou moins,
    éventuellement au moins un élément choisi parmi
    Nb : 0,005 % ou plus et 0,4 % ou moins, B : 0,0002 % ou plus et 0,0020 % ou moins, Cu : 0,005 % ou plus et 0,2 % ou moins, Ni : 0,005 % ou plus et 0,2 % ou moins, Cr : 0,005 % ou plus et 0,4 % ou moins, Mo : 0,005 % ou plus et 0,4 % ou moins, Ca : 0,0002 % ou plus et 0,01 % ou moins et terres rares : 0,0002 % ou plus et 0,01 % ou moins, et
    le reste étant du Fe et des impuretés inévitables incluant Sb : 0,01 % ou moins, Sn : 0,1 % ou moins et Zn : 0,01 % ou moins, et
    la microstructure comprenant une phase principale et une phase secondaire,
    la phase principale étant une phase bainite ayant une fraction surfacique supérieure à 85 %,
    la phase secondaire étant l'une au moins d'une phase ferrite, d'une phase martensite et d'une phase austénite résiduelle, la phase secondaire ayant une fraction surfacique de 0 % ou plus et moins de 15 % au total,
    la phase bainite ayant un intervalle de latte moyen entre lattes de 400 nm ou moins, et les lattes ayant une longueur moyenne d'axe long de 5,0 µm ou moins.
  2. Procédé de fabrication d'une tôle d'acier laminée à chaud hautement résistante, comprenant :
    le chauffage d'un matériau d'acier ayant la composition selon la revendication 1 à 1200 °C ou plus,
    l'application d'un laminage à chaud ayant un laminage de dégrossissage et un laminage de finissage, le laminage de finissage ayant une réduction cumulée par laminage de 50 % ou plus sur une plage de température de 1000 °C ou moins et une température de finissage et 820 °C ou plus et 930 °C ou moins,
    le début du refroidissement dans un délai de 4,0 s après le laminage à chaud,
    la réalisation d'un refroidissement à une vitesse de refroidissement de 20 °C/s ou plus, et
    la réalisation d'un enroulement à une température d'enroulement de 300 °C ou plus et 450 °C ou moins.
EP14785555.5A 2013-04-15 2014-03-17 Tôle d'acier à haute résistance mécanique laminée à chaud et son procédé de production Active EP2987887B1 (fr)

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JP2013084448A JP5867444B2 (ja) 2013-04-15 2013-04-15 靭性に優れた高強度熱延鋼板およびその製造方法
JP2013084450A JP5870955B2 (ja) 2013-04-15 2013-04-15 穴拡げ加工性に優れた高強度熱延鋼板およびその製造方法
PCT/JP2014/001509 WO2014171063A1 (fr) 2013-04-15 2014-03-17 Tôle d'acier à haute résistance mécanique laminée à chaud et son procédé de production

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Families Citing this family (31)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10138536B2 (en) * 2012-01-06 2018-11-27 Jfe Steel Corporation High-strength hot-rolled steel sheet and method for producing same
WO2014148001A1 (fr) 2013-03-19 2014-09-25 Ｊｆｅスチール株式会社 TÔLE D'ACIER LAMINÉE À CHAUD À HAUTE RÉSISTANCE QUI PRÉSENTE UNE RÉSISTANCE À LA TRACTION ÉGALE OU SUPÉRIEURE À 780 MPa
EP3112488B1 (fr) * 2014-02-27 2019-05-08 JFE Steel Corporation Tôle d'acier laminée à chaud à haute résistance et son procédé de fabrication
KR102090884B1 (ko) 2015-07-27 2020-03-18 제이에프이 스틸 가부시키가이샤 고강도 열연 강판 및 그 제조 방법
US10870901B2 (en) * 2015-09-22 2020-12-22 Tata Steel Ijmuiden B.V. Hot-rolled high-strength roll-formable steel sheet with excellent stretch-flange formability and a method of producing said steel
WO2017168436A1 (fr) * 2016-03-30 2017-10-05 Tata Steel Limited Produit d'acier haute résistance laminé à chaud (hrhss) ayant une résistance à la traction de 1000 à 1200 mpa et un allongement total de 16 % à 17 %
CN105734423B (zh) * 2016-04-27 2018-08-10 宝山钢铁股份有限公司 一种1180MPa级析出强化型热轧超高强钢及其制造方法
CN105925887B (zh) * 2016-06-21 2018-01-30 宝山钢铁股份有限公司 一种980MPa级热轧铁素体贝氏体双相钢及其制造方法
CN106498287B (zh) * 2016-12-15 2018-11-06 武汉钢铁有限公司 一种ct90级连续管用热轧钢带及其生产方法
WO2018150955A1 (fr) * 2017-02-17 2018-08-23 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud de haute résistance et son procédé de fabrication
CN107151763B (zh) * 2017-05-27 2019-03-26 武汉钢铁有限公司 薄规格高强度冷成型用热轧钢带及其生产方法
CN107916369A (zh) * 2017-11-08 2018-04-17 河钢股份有限公司 一种q590级高强韧性热轧钢带及其制备方法
WO2020026593A1 (fr) * 2018-07-31 2020-02-06 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute résistance et son procédé de fabrication
CN112513308A (zh) * 2018-07-31 2021-03-16 杰富意钢铁株式会社 高强度热轧镀覆钢板
CN112601831B (zh) * 2018-08-23 2022-05-31 杰富意钢铁株式会社 方形钢管及其制造方法以及建筑构造物
WO2020065381A1 (fr) * 2018-09-28 2020-04-02 Arcelormittal Tôle d'acier laminée à chaud et son procédé de fabrication
HUE053584T2 (hu) * 2018-11-14 2021-07-28 Ssab Technology Ab Melegen hengerelt acél szalag és eljárás az elõállítására
CN109930070B (zh) * 2019-03-28 2020-02-14 北京科技大学 一种利用稀土提高低碳当量钢板焊接热影响区韧性的方法
KR102221452B1 (ko) * 2019-05-03 2021-03-02 주식회사 포스코 전단가공성이 우수한 초고강도 강판 및 그 제조방법
JP6973681B2 (ja) * 2019-11-20 2021-12-01 Ｊｆｅスチール株式会社 電縫鋼管用熱延鋼板およびその製造方法、電縫鋼管およびその製造方法、ラインパイプ、建築構造物
EP4074854A4 (fr) * 2019-12-09 2023-01-04 Nippon Steel Corporation Plaque d'acier laminée à chaud
WO2021117705A1 (fr) * 2019-12-09 2021-06-17 日本製鉄株式会社 Plaque d'acier laminée à chaud
US20230045924A1 (en) * 2019-12-20 2023-02-16 Tata Steel Ijmuiden B.V. Hot rolled high strength steel strip having high hole expansion ratio
CN114107785B (zh) * 2020-08-27 2022-10-21 宝山钢铁股份有限公司 一种具有超高屈强比的吉帕级贝氏体钢及其制造方法
CN114107791B (zh) * 2020-08-31 2023-06-13 宝山钢铁股份有限公司 一种980MPa级全贝氏体型超高扩孔钢及其制造方法
KR102418263B1 (ko) * 2020-11-05 2022-07-08 주식회사 포스코 성형성이 우수한 열연강판 및 그 제조방법
KR102403648B1 (ko) * 2020-11-17 2022-05-30 주식회사 포스코 고강도 열연강판, 열연 도금강판 및 이들의 제조방법
CN112642860A (zh) * 2020-12-03 2021-04-13 攀钢集团攀枝花钢铁研究院有限公司 一种if钢的热轧方法
CN113025894A (zh) * 2021-02-22 2021-06-25 北京科技大学 一种短流程工艺在线生产的超高强q960热轧卷板及制备方法
CN115679191B (zh) * 2021-07-28 2023-09-12 宝山钢铁股份有限公司 一种550MPa级耐候桥梁钢及制造方法
KR20230094376A (ko) * 2021-12-21 2023-06-28 주식회사 포스코 점용접성이 우수한 고강도 고성형성 강판 및 그 제조방법

Family Cites Families (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6254698B1 (en) * 1997-12-19 2001-07-03 Exxonmobile Upstream Research Company Ultra-high strength ausaged steels with excellent cryogenic temperature toughness and method of making thereof
US6364968B1 (en) * 2000-06-02 2002-04-02 Kawasaki Steel Corporation High-strength hot-rolled steel sheet having excellent stretch flangeability, and method of producing the same
JP3947354B2 (ja) 2000-12-07 2007-07-18 新日本製鐵株式会社 穴拡げ性と延性に優れた高強度熱延鋼板及びその製造方法
JP4317419B2 (ja) 2003-10-17 2009-08-19 新日本製鐵株式会社 穴拡げ性と延性に優れた高強度薄鋼板
JP4692015B2 (ja) * 2004-03-30 2011-06-01 Ｊｆｅスチール株式会社 伸びフランジ性と疲労特性に優れた高延性熱延鋼板およびその製造方法
KR100937809B1 (ko) * 2005-03-31 2010-01-20 제이에프이 스틸 가부시키가이샤 열연강판, 그 제조방법 및 열연강판성형체
JP4630158B2 (ja) 2005-08-23 2011-02-09 株式会社神戸製鋼所 低降伏比高強度高靭性鋼板の製造方法
KR20080110904A (ko) * 2006-05-16 2008-12-19 제이에프이 스틸 가부시키가이샤 신장 특성, 신장 플랜지 특성 및 인장 피로 특성이 우수한 고강도 열연강판 및 그 제조 방법
JP5277672B2 (ja) * 2007-03-29 2013-08-28 Ｊｆｅスチール株式会社 耐遅れ破壊特性に優れた高張力鋼板ならびにその製造方法
US8582694B2 (en) * 2007-04-30 2013-11-12 Scott R. Velazquez Adaptive digital receiver
CA2844718C (fr) * 2009-01-30 2017-06-27 Jfe Steel Corporation Tole epaisse laminee a chaud en acier a haute resistance a la traction presentant une excellente tenacite a basse temperature et processus pour sa production
JP5195469B2 (ja) 2009-01-30 2013-05-08 Ｊｆｅスチール株式会社 低温靭性に優れた厚肉高張力熱延鋼板の製造方法
CA2750291C (fr) * 2009-01-30 2014-05-06 Jfe Steel Corporation Tole forte d'acier laminee a chaud a resistance elevee a la traction presentant une excellente resistance de hic et son procede de fabrication
JP4978741B2 (ja) * 2010-05-31 2012-07-18 Ｊｆｅスチール株式会社 伸びフランジ性および耐疲労特性に優れた高強度熱延鋼板およびその製造方法
JP5029748B2 (ja) 2010-09-17 2012-09-19 Ｊｆｅスチール株式会社 靭性に優れた高強度熱延鋼板およびその製造方法
JP5126326B2 (ja) * 2010-09-17 2013-01-23 Ｊｆｅスチール株式会社 耐疲労特性に優れた高強度熱延鋼板およびその製造方法
JP5029749B2 (ja) * 2010-09-17 2012-09-19 Ｊｆｅスチール株式会社 曲げ加工性に優れた高強度熱延鋼板およびその製造方法
JP5724267B2 (ja) * 2010-09-17 2015-05-27 Ｊｆｅスチール株式会社 打抜き加工性に優れた高強度熱延鋼板およびその製造方法
US9587287B2 (en) * 2011-03-31 2017-03-07 Nippon Steel and Sumitomo Metal Corporation Bainite-containing-type high-strength hot-rolled steel sheet having excellent isotropic workability and manufacturing method thereof
JP5605310B2 (ja) * 2011-06-07 2014-10-15 新日鐵住金株式会社 鋼材および衝撃吸収部材
US8810566B2 (en) * 2011-07-15 2014-08-19 Disney Enterprises, Inc. Providing a navigation mesh by which objects of varying sizes can traverse a virtual space

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

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US20160076124A1 (en) 2016-03-17
MX2020003923A (es) 2020-08-13
EP2987887A4 (fr) 2016-09-14
MX2015014437A (es) 2016-02-03
EP2987887A1 (fr) 2016-02-24
WO2014171063A1 (fr) 2014-10-23
KR20160041850A (ko) 2016-04-18
CN105102662A (zh) 2015-11-25

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