EP2796584A1 - Feuille d'acier à haute résistance et son procédé de fabrication - Google Patents

Feuille d'acier à haute résistance et son procédé de fabrication Download PDF

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Publication number
EP2796584A1
EP2796584A1 EP12860717.3A EP12860717A EP2796584A1 EP 2796584 A1 EP2796584 A1 EP 2796584A1 EP 12860717 A EP12860717 A EP 12860717A EP 2796584 A1 EP2796584 A1 EP 2796584A1
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EP
European Patent Office
Prior art keywords
less
ferrite
steel sheet
strength steel
pearlite
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.)
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EP12860717.3A
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German (de)
English (en)
Other versions
EP2796584A4 (fr
EP2796584B1 (fr
Inventor
Kouichi Nakagawa
Kenji Kawamura
Takeshi Yokota
Kazuhiro Seto
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JFE Steel Corp
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JFE Steel Corp
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Publication of EP2796584A4 publication Critical patent/EP2796584A4/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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • 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
    • C22C38/02—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
    • 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
    • C21D1/26—Methods of annealing
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to high-strength steel sheets, having excellent formability, applicable to automotive parts and particularly relates to a high-strength steel sheet having a tensile strength TS of 600 MPa to 700 MPa, an elongation El of 25% or more (in the case of a JIS #5 test specimen with a thickness of 1.6 mm), and a hole expansion ratio ⁇ of 80% or more, the hole expansion ratio ⁇ being an indicator for stretch flangeability, and a method for producing the same.
  • gauge reduction and weight reduction have been investigated by increasing the strength of steel sheets which are materials of automotive parts.
  • the increase in strength of steel sheets generally causes the reduction in ductility thereof; hence, high-strength steel sheets having both high strength and good formability are strongly needed.
  • Patent Literature 1 discloses a high-strength steel sheet, having an excellent strength-hole expansion ratio balance and excellent shape fixability, for forming.
  • the steel sheet contains 0.02% to 0.16% C, 0.010% or less P, 0.003% or more S, 0.2% to 4% one or both of Si and Al in total, and 0.5% to 4% one or more of Mn, Ni, Cr, Mo, and Cu in total as chemical components on a mass basis, the remainder being Fe and inevitable impurities, C / (Si + Al + P) being 0.1 or less.
  • the cross-sectional microstructure of the steel sheet contains one or both of martensite and retained austenite, the sum of the area fraction of martensite and the area fraction of retained austenite being less than 3%, and one or both of ferrite and bainite, the sum of the area fraction of ferrite and the area fraction of bainite being 80% or more, the remainder being pearlite.
  • the maximum length of pearlite, martensite, and retained austenite is 10 microns or less.
  • the number of inclusions, having a size of 20 microns or more, present in a cross section of the steel sheet is 0.3 or less per square millimeter.
  • Patent Literature 2 discloses a hot-rolled steel containing 0.05% to less than 0.15% C, 0.8% to 1.2% Mn, 0.02% to 2.0% Si, 0.002% to less than 0.05% sol. Al, and 0.001%% to less than 0.005% N on a mass basis, the remainder being Fe and impurities. Each of Ti, Nb, and V in the impurities is less than 0.005%.
  • the hot-rolled steel has a microstructure containing ferrite with an average grain size of 1.1 ⁇ m to 5.0 ⁇ m as a primary phase and one or both of pearlite and cementite as a secondary phase and satisfies the inequality Mn ⁇ / Mon ⁇ ⁇ 1, where Mn ⁇ is the content of Mn in cementite in pearlite containing cementite and Mn ⁇ is the content of Mn in ferrite.
  • Patent Literature 3 discloses a method for producing a hot-rolled steel sheet in which the structural fraction of cementite with an equivalent circle radius of 0.1 ⁇ m or more is 0.1% or less and/or the structural fraction of martensite is 5% or less and which has a tensile strength of 50 kgf/mm 2 or more, stretch flangeability corresponding to a hole expansion ratio of 1.8 or more, and excellent ductility.
  • the inventors have investigated a high-strength steel sheet targeted as described above and have found that it is effective to form a microstructure which contains ferrite and pearlite and in which the volume fraction of ferrite is 70% to 97%, the volume fraction of pearlite is 3% or more, the volume fraction of cementite present at ferrite grain boundaries is 2% or less, the sum of the volume fractions of the other phases is less than 3% or less, and the average grain size of ferrite is 7 ⁇ m or less.
  • the present invention has been made on the basis of this finding and provides a high-strength steel sheet having a composition containing 0.10% to 0.18% C, more than 0.5% to 1.5% Si, 0.5% to 1.5% Mn, 0.05% or less P, 0.005% or less S, and 0.05% or less Al on a mass basis, the remainder being Fe and inevitable impurities, and also having a microstructure containing ferrite and pearlite.
  • the volume fraction of the ferrite is 70% to 97%.
  • the volume fraction of the pearlite is 3% or more.
  • the volume fraction of cementite present at grain boundaries of the ferrite is 2% or less.
  • the sum of the volume fractions of phases other than the ferrite, the pearlite, and the cementite is less than 3%.
  • the average grain size of the ferrite is 7 ⁇ m or less.
  • the high-strength steel sheet according to the present invention preferably further contains at least one selected from the group consisting of 0.01% to 1.0% Cr, 0.01% to 0.1% Ti, and 0.01% to 0.1% V on a mass basis.
  • the high-strength steel sheet according to the present invention preferably has a tensile strength TS of 600 MPa to 700 MPa.
  • the high-strength steel sheet according to the present invention preferably has a hole expansion ratio ⁇ of 80% or more.
  • the volume fraction of the ferrite is preferably 80% to 95%.
  • the volume fraction of the pearlite is preferably 3% to 30%. In the high-strength steel sheet according to the present invention, the volume fraction of the pearlite is preferably 5% to 28%.
  • a method for producing a high-strength steel sheet according to the present invention includes a step of preparing a steel slab having a chemical composition containing 0.10% to 0.18% C, more than 0.5% to 1.5% Si, 0.5% to 1.5% Mn, 0.05% or less P, 0.005% or less S, and 0.05% or less Al on a mass basis, the remainder being Fe and inevitable impurities; a step of hot-rolling the steel slab into a hot-rolled sheet; and a step of annealing the hot-rolled sheet in such a way that the hot-rolled sheet is heated to a two-phase temperature range between the Ac 1 transformation temperature and the Ac 3 transformation temperature, is cooled to a temperature range of 450°C to 600°C at an average cooling rate of 5 °C/s to 30 °C/s, and is then held at this temperature range for 100 s or more.
  • the steel slab preferably further contains at least one selected from the group consisting of 0.01% to 1.0% Cr, 0.01% to 0.1% Ti, and 0.01% to 0.1% V on a mass basis.
  • the annealing step preferably includes heating to the two-phase temperature range between the Ac 1 transformation temperature and the Ac 3 transformation temperature, cooling to a temperature range of 450°C to 600°C at an average cooling rate of 10 °C/s to 20 °C/s, and then holding at this temperature range for 100 s to 300 s.
  • a high-strength steel sheet excellent in formability, having a TS of 600 MPa to 700 MPa, an El of 25% or more, and a ⁇ of 80% or more can be produced.
  • the unit "%" for the content of an element component hereinafter refers to mass percent.
  • C forms a secondary phase such as pearlite, microstructure, or cementite to contribute to increasing the strength of the steel sheet.
  • the content of C needs to be 0.10% or more.
  • the C content is more than 0.18%, the amount of the secondary phase is too large; hence, TS exceeds 700 MPa or El or ⁇ is reduced. Therefore, the C content is 0.10% to 0.18%.
  • the C content is preferably 0.12% to 0.16%.
  • Si is an element contributing to solid solution hardening. In order to achieve a TS of 600 MPa or more, the content of Si needs to be more than 0.5%. However, when the Si content is more than 1.5%, surface properties of the steel sheet are impaired by scaling. Therefore, the Si content is more than 0.5% to 1.5%.
  • the Si content is preferably 0.7% to 1.2%.
  • Mn is an element contributing to solid solution hardening. In order to achieve a TS of 600 MPa or more, the content of Mn needs to be 0.5% or more. However, when the Mn content is more than 1.5%, TS exceeds 700 MPa or a reduction in ⁇ is caused by segregation. Therefore, the Mn content is 0.5% to 1.5%. The Mn content is preferably 1.1% to 1.5%.
  • P is an element contributing to solid solution hardening.
  • the content of P is more than 0.05%, a reduction in El is caused by segregation. Therefore, the P content is 0.05% or less.
  • the P content is preferably 0.03% or less.
  • the S content of S is more than 0.005%, S segregates at prior-austenite grain boundaries or Mn precipitates in the steel sheet to cause a reduction in ⁇ . Therefore, the S content is 0.005% or less and is preferably low.
  • Al is added to steel as a deoxidizer and is an element effective in enhancing the cleanliness of steel.
  • the content of Al is more than 0.05%, a large number of inclusions are caused, thereby causing surface defects of the steel sheet. Therefore, the Al content is 0.05% or less.
  • the Al content is preferably 0.03% or less.
  • the remainder is Fe and inevitable impurities.
  • At least one selected from the group consisting of 0.01% to 1.0% Cr, 0.01% to 0.1% Ti, and 0.01% to 0.1% V may be contained. This is because Cr, Ti, and V have a function of suppressing the recrystallization and recovery of austenite in a hot-rolling temperature range, promoting the grain refining of ferrite, forming a carbide, or strengthening ferrite in a solid solution state.
  • Nb is an element for achieving a similar effect. The addition of these elements does not significantly reduce the elongation (El) as compared to the addition of the same amount of Nb. It is preferred that C is 0.02% to 0.5%, Ti is 0.02% to 0.05%, and V is 0.02% to 0.05%.
  • the inevitable impurities are, for example, O, which is 0.003% or less, Cu, Ni, Sn, and Sb, which are 0.05% or less.
  • a microstructure containing ferrite and pearlite is formed.
  • volume fraction of ferrite in the microstructure is less than 70%, TS exceeds 700 MPa or a ⁇ of 80% or more is not achieved. In contrast, when the volume fraction thereof is more than 97%, a TS of 600 MPa is not achieved because the amount of pearlite is reduced. Therefore, the volume fraction of ferrite is 70% to 97%.
  • the volume fraction of ferrite is preferably 95% or less and more preferably 80% to 90%.
  • volume fraction of pearlite 3% or more
  • the volume fraction of pearlite is preferably 5% or more. This is probably because pearlite is soft as compared to cementite, martensite, and retained austenite and therefore the number of voids caused at the interface between ferrite and pearlite is small as compared to the number of voids caused at the interface between ferrite and martensite and the interface between ferrite and retained austenite after forming.
  • volume fraction of cementite present at ferrite grain boundaries 2% or less
  • the steel sheet according to the present invention may possibly contain cementite, martensite, and the like in addition to ferrite and pearlite.
  • the volume fraction of cementite, particularly cementite present at ferrite grain boundaries, in the microstructure is more than 2%, the number of voids caused at the interface between ferrite and cementite during hole expansion is increased and therefore a reduction in ⁇ is caused.
  • the volume fraction of the cementite present at the ferrite grain boundaries is 2% or less.
  • the volume fraction thereof may be 0%.
  • Phases other than ferrite, pearlite, and the cementite present at the ferrite grain boundaries are martensite, retained austenite, and the like.
  • the sum of the volume fractions of these phases in the microstructure is less than 3%, required properties of the steel sheet are not significantly affected. Therefore, the sum of the volume fractions of the phases other than ferrite, pearlite, and the cementite present at the ferrite grain boundaries is less than 3%.
  • the sum thereof is preferably 2.5% or less and may be 0%.
  • Average grain size of ferrite 7 ⁇ m or less
  • the average grain size of ferrite is 7 ⁇ m or less.
  • the average grain size of ferrite is preferably 5 ⁇ m or less.
  • the volume fraction of each of ferrite, pearlite, cementite, martensite, and retained austenite in the microstructure is determined in such a way that a thickness-wise cross-section of the steel sheet that is parallel to the rolling direction of the steel sheet is polished and is subsequently corroded with nital, three fields of view are photographed at 1,000 times magnification using an optical microscope, and the types of structures are identified by image processing. Furthermore, the average grain size of ferrite is also calculated by an intercept method.
  • orthogonal line segments are drawn so as to longitudinally divide an image (corresponding to 84 ⁇ m in the rolling direction and 65 ⁇ m in the thickness direction) photographed at 1,000 times magnification using the optical microscope into 20 parts and so as to laterally divide the image into 20 parts, a value obtained by dividing the sum of the lengths of ferrite grains cut by one of the line segments by the number of the ferrite grains is defined as the cut length, and the average intercept length L is calculated for each line segment.
  • the volume fraction of the cementite present at the ferrite grain boundaries in the microstructure is determined in such a way that three fields of view are photographed at 3,000 times magnification using a scanning electron microscope and the cementite present at the ferrite grain boundaries is extracted by image processing.
  • a steel slab used is preferably produced by a continuous casting process for the purpose of preventing the macro-segregation of components of molten steel, produced by a known process using a converter or the like, having the above composition and may be produced by a ingot-casting process.
  • Hot rolling The steel slab produced as described above is reheated in a furnace after being cooled to room temperature or without being cooled to room temperature or is held at high temperature without being fed through a furnace and is then hot-rolled.
  • Hot-rolling conditions are not particularly limited. It is preferred that after the steel slab is heated to a temperature of 1,100°C to 1,300°C, hot rolling (finish rolling) is completed at 850°C to 950°C and the steel slab is coiled at 720°C or lower. This is due to reasons below. That is, when the heating temperature is lower than 1,100°C, the deformation resistance of steel is high and therefore hot rolling may possibly be difficult. When the heating temperature is higher than 1,300°C, crystal grains become coarse and therefore TS may possibly be reduced.
  • finishing delivery temperature When the finishing delivery temperature is lower than 850°C, ferrite is produced during rolling; hence, extended ferrite is formed and a reduction in ⁇ may possibly be caused.
  • finishing delivery temperature is higher than 950°C, crystal grains become coarse and therefore TS may possibly be reduced.
  • the coiling temperature is higher than 720°C, the formation of an internal oxidation layer is significant and therefore chemical treatability and post-painting corrosion resistance may possibly be deteriorated.
  • a hot-rolled sheet is pickled for the purpose of removing scale formed on the surface of the steel sheet.
  • Annealing The pickled hot-rolled sheet is annealed in such a way that the hot-rolled sheet is heated to a two-phase temperature range between the Ac 1 transformation temperature and the Ac 3 transformation temperature, is cooled to a temperature range of 450°C to 600°C at an average cooling rate of 5 °C/s to 30 °C/s, and is then held at this temperature range for 100 s or more.
  • the reason for heating the hot-rolled sheet to the two-phase temperature range between the Ac 1 transformation temperature and the Ac 3 transformation temperature is to form the microstructure containing ferrite and pearlite is formed.
  • the reason for cooling the hot-rolled sheet to a temperature range of 450°C to 600°C at an average cooling rate of 5 °C/s to 30 °C/s is as follows: when the cooling temperature is higher than 600°C, the volume fraction of the cementite present at the ferrite grain boundaries exceeds 2% and therefore target ⁇ is not achieved; when the cooling temperature is lower than 450°C, the amount of martensite is increased and therefore TS exceeds 700 MPa or ⁇ is reduced; when the average cooling rate is less than 5 °C/s, the ferrite grains become coarse and therefore a TS of 600 MPa is not achieved; and when the average cooling rate is more than 30 °C/s, the volume fraction of the cementite present at the ferrite grain boundaries exceeds 2% and therefore a ⁇ of 80% or more is not achieved.
  • the average cooling rate is preferably 10 °C/s to 20 °C/s.
  • the reason for holding the hot-rolled sheet at a temperature of 450°C to 600°C for 100 s or more is that when the residence time is less than 100 s, the amount of pearlite is reduced and therefore ⁇ is reduced.
  • the residence time is more preferably 150 s or more.
  • the residence time is preferably 300 s or less from the viewpoint of production efficiency because an effect due to residence for an excessively long time is saturated. Annealing can be performed using a continuous annealing line.
  • the steel sheet obtained as described above was investigated for microstructure by the above-mentioned method and was subjected to a tensile test using a JIS #5 test specimen in accordance with JIS Z 2241, whereby TS and El were determined. Furthermore, a hole expansion test was performed using a 100 mm square test specimen in accordance with The Japan Iron and Steel Federation standard JFST 1001-1996, whereby ⁇ was determined.
  • steel sheets of examples of the present invention all have a TS of 600 MPa to 700 MPa, an El of 25% or more, a ⁇ of 80% or more and are high-strength steel sheets with excellent formability.
  • steel sheets of comparative examples do not have a target TS or ⁇ .

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  • Chemical & Material Sciences (AREA)
  • 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)
  • Heat Treatment Of Steel (AREA)
EP12860717.3A 2011-12-19 2012-11-29 Feuille d'acier à haute résistance et son procédé de fabrication Not-in-force EP2796584B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2011276997A JP5316634B2 (ja) 2011-12-19 2011-12-19 加工性に優れた高強度鋼板およびその製造方法
PCT/JP2012/007663 WO2013094130A1 (fr) 2011-12-19 2012-11-29 Feuille d'acier à haute résistance et son procédé de fabrication

Publications (3)

Publication Number Publication Date
EP2796584A1 true EP2796584A1 (fr) 2014-10-29
EP2796584A4 EP2796584A4 (fr) 2015-10-14
EP2796584B1 EP2796584B1 (fr) 2018-03-07

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EP12860717.3A Not-in-force EP2796584B1 (fr) 2011-12-19 2012-11-29 Feuille d'acier à haute résistance et son procédé de fabrication

Country Status (7)

Country Link
US (1) US20140332123A1 (fr)
EP (1) EP2796584B1 (fr)
JP (1) JP5316634B2 (fr)
KR (1) KR101624439B1 (fr)
CN (1) CN104011240B (fr)
IN (1) IN2014KN01170A (fr)
WO (1) WO2013094130A1 (fr)

Cited By (1)

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KR101624439B1 (ko) 2016-05-25
CN104011240A (zh) 2014-08-27
EP2796584B1 (fr) 2018-03-07
IN2014KN01170A (fr) 2015-10-16
JP2013127099A (ja) 2013-06-27
KR20140100994A (ko) 2014-08-18
WO2013094130A1 (fr) 2013-06-27
JP5316634B2 (ja) 2013-10-16
CN104011240B (zh) 2016-11-23
US20140332123A1 (en) 2014-11-13

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