EP2806042B1 - Procédé de production de plaque conique - Google Patents

Procédé de production de plaque conique Download PDF

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Publication number
EP2806042B1
EP2806042B1 EP12865903.4A EP12865903A EP2806042B1 EP 2806042 B1 EP2806042 B1 EP 2806042B1 EP 12865903 A EP12865903 A EP 12865903A EP 2806042 B1 EP2806042 B1 EP 2806042B1
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EP
European Patent Office
Prior art keywords
less
content
toughness
plate
case
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EP12865903.4A
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German (de)
English (en)
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EP2806042A1 (fr
EP2806042A4 (fr
Inventor
Tomoyuki Yokota
Masayoshi Nakamura
Kazukuni Hase
Shinji Mitao
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JFE Steel Corp
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JFE Steel Corp
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Priority claimed from JP2012007765A external-priority patent/JP5772620B2/ja
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys 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
    • 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
    • C22C38/02—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
    • C22C38/08—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
    • C22C38/16—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

Definitions

  • the present invention relates to a method for manufacturing a tapered plate (also called a tapered steel plate or a LP steel plate (Longitudinally Profiled Steel Plate)) whose plate thickness continuously changes in the longitudinal direction which can be preferably used for shipbuilding or the architecture, for example, and relates to a method for manufacturing a tapered plate having a tensile strength of 570 MPa or more and a difference in thickness between a thicker portion and a thinner portion (a difference of steel plate thickness) in the longitudinal direction of 10 mm or more which has only a small difference in strength throughout the steel plate and can be subjected to high-heat input welding with a welding heat input of more than 300 kJ/cm.
  • a thick steel plate has a shape which is uniform in both the width and longitudinal directions.
  • This kind of thick steel plate is called a tapered plate, a tapered steel plate, a LP steel plate or the like, and there have been many proposals regarding the method for manufacturing a tapered plate such as those disclose in Patent Literature 1, Patent Literature 2 and Patent Literature 3. These proposals are intended to show how to manufacture a tapered plate with high dimensional accuracy.
  • the steel plate cannot be used in practice.
  • TMCP Thermo-Mechanical Control Process
  • austenite + ferrite dual phase temperature range
  • subsequent transformation from austenite to ferrite ferrite transformation
  • Patent Literature 4 discloses a method for cooling a tapered plate, in order to achieve uniform material properties, the method including measuring a temperature distribution in the longitudinal direction before cooling is performed, calculating optimum cooling conditions at respective positions on the basis of the measured temperature distribution and adjusting conveyance speed in cooling in accordance with a plate thickness.
  • Patent Literature 5 discloses a method for cooling a tapered plate, the method including starting cooling the thinner portion and the thicker portion of the steel plate at the same time and changing the time at which the portions leave a cooling apparatus in accordance with their thicknesses, or the method including starting cooling sequentially in order of distance in the longitudinal direction of the steel plate and stopping cooling at the same time. Both of the proposals are intended to decrease the variation of material properties in a steel plate when accelerated cooling is performed.
  • Patent Literature 6 an example of approaches to solve the problem described above, which controls a chemical composition of the steel plate, is described in Patent Literature 6.
  • this technique it is disclosed that the scatter of strength can be decreased by increasing Nb content up to 0.015% to 0.06%.
  • Patent Literature 8 discloses the manufacture of a steel plate with varying thickness containing C, Si, Mn, Cu, Ni, Cr, Mo, V, B, Nb and Ti in a suitable ratio used for construction of ship, building, etc..
  • the manufacturing method involves tempering where holding time and temperature for the maximum thick part is based on a temperature rise curve.
  • An object of the present invention is, by advantageously solving the problems described above, to provide a method for manufacturing a tapered plate having a difference in thickness (taper amount) between a thicker portion and a thinner portion in the longitudinal direction of 10 mm or more, which has a tensile strength of 570 MPa or more and a small scatter of strength, and which is excellent in terms of toughness in a weld zone formed by performing high-heat input welding with a heat input of more than 300 kJ/cm.
  • the present inventors conducted investigations regarding the influence of the contents of Ti and N on a difference in strength between a thicker portion and a thinner portion of B containing tapered plates having various contents of Ti and N, and found that, in the case where the contents of Ti and N satisfy the relationship 0 ⁇ N - Ti/3.42 ⁇ 0.0025, since an appropriate amount of solid solute B is stably achieved, there is a decrease in difference in strength between a thicker portion and a thinner portion.
  • a tapered plate having a difference in thickness (taper amount) between a thicker portion and a thinner portion of 10 mm or more, which has a tensile strength of 570 MPa or more and small difference in strength between a thicker portion and a thinner portion, and which can be subjected to high-heat input welding such as submerged arc welding, electrogas arc welding and electroslag welding, which results in a great advantage in industry.
  • the C is added in an amount of 0.03% or more in order to achieve strength required for structural steel.
  • the C content is set to be 0.03% or more and 0.12% or less, preferably 0.04% to 0.09%.
  • Si 0.03% or more and 0.5% or less
  • Si is added in an amount of 0.03% or more for the purpose of deoxidation and achieving strength.
  • the Si content is set to be 0.5% or less, preferably 0.4% or less.
  • Mn 0.8% or more and 2.2% or less
  • Mn is added in an amount of 0.8% or more in order to achieve strength of a base metal.
  • the Mn content is set to be 0.8% or more and 2.2% or less, preferably 1.2% to 2.0%.
  • the P content is an inevitable impurity in the present invention.
  • the P content is set to be 0.015% or less, preferably 0.012% or less.
  • S content is 0.0005% or more in order to form CaS and MnS.
  • the S content is set to be 0.0005% or more and 0.0050 or less.
  • Al 0.005% or more and 0.1% or less
  • Al content is 0.005% or more for the purpose of deoxidation of steel.
  • the Al content is set to be 0.005% or more and 0.1% or less, preferably 0.01% to 0.06%.
  • Nb 0.003% or more and 0.014% or less
  • Nb is effective for achieving strength and toughness of a base metal and strength of a weld joint and it is necessary that the Nb content be 0.003% or more in order to realize these effects, since there is a decrease in the toughness of a welded heat affected zone formed as a result of performing high-heat input welding in the case where the Nb content is more than 0.014%, the Nb content is set to be 0.003% or more and 0.014% or less, preferably 0.005% to 0.013%.
  • Ti is added in an amount of 0.003% or more, since Ti increases toughness of a base metal by precipitating in a form of TiN at a time of solidification so as to prevent an increase in an austenite grain size in a welded heat affected zone and by providing the nuclei of ferrite transformation so as to precipitate ferrite grains.
  • the Ti content is set to be 0.003% or more and 0.02% or less, preferably 0.005% to 0.018%.
  • B increases the strength of a base metal by forming solid solute B so as to increase hardenability
  • B increases the toughness of a base metal by forming BN in a welded heat affected zone so as to decrease the amount of solid solute N and by providing nuclei of ferrite transformation so as to form ferrite grains, B is added in an amount of 0.0003% or more.
  • the B content is set to be 0.0003% or more and 0.0025% or less, preferably 0.0005% to 0.0022%.
  • N 0.0030% or more and 0.0070% or less
  • the N content is set to be 0.0030% or more.
  • the N content is set to be 0.0030% or more and 0.0070% or less.
  • Ca increases the toughness of a welded heat affected zone when high-heat input welding is performed, since there is an increase in frequency of nuclei formation of ferrite grains as a result of formation of MnS, TiN and BN on CaS.
  • the Ca content is set to be 0.0005% or more in order to realize this effect.
  • the Ca content is set to be 0.0005% or more and 0.0050% or less, preferably 0.0005% to 0.0030%, more preferably 0.0007% to 0.0030%.
  • the chemical composition described above is the base chemical composition of the present invention and a sufficient effect can be realized with this chemical composition, in order to further improve the properties, one, two or more of Cu, Ni, Cr, Mo, V, Mg, Zr and REM may be added.
  • the Cu is effective for increasing the strength of a base metal, and it is preferable that the Cu content be 0.05% or more in order to realize this effect, but, in the case where the Cu content is more than 1.0%, there is deterioration of the surface quality of a steel plate due to occurrence of hot shortness. Therefore, in the case where Cu is added, it is preferable that the Cu content be 1.0% or less, more preferably 0.1% to 0.8%.
  • Ni 0.05% or more and 1:0% or less
  • Ni increases the strength of a base metal while maintaining high toughness of the base metal
  • the Ni content be 0.05% or more in order to realize this effect.
  • the Ni content in the case where the Ni content is more than 1.0%, since the effect becomes saturated, in the case where Ni is added, it is preferable that the Ni content be 0.05% or more and 1.0% or less, more preferably 0.1% to 0.9%.
  • Cr is effective for increasing the strength of a base metal and it is preferable that the Cr content be 0.05% or more in order to realize this effect, but, in the case where the Cr content is excessively large, there is a decrease in toughness. Therefore, in the case where Cr is added, it is preferable that the Cr content be 0.5% or less, more preferably 0.1% to 0.4%.
  • Mo is effective for increasing the strength of a base metal and it is preferable that the Mo content be 0.05% or more in order to realize this effect, but there is a decrease in toughness in the case where the Mo content is excessively large. Therefore, in the case where Mo is added, it is preferable that the Mo content be 0.5% or less, more preferably 0.07% to 0.4%.
  • V 0.02% or more and 0.1% or less
  • V is effective for increasing the strength of a base metal and it is preferable that the V content be 0.02% or more in order to realize this effect, but there is a decrease in toughness in the case where the V content is more than 0.1%. Therefore, in the case where V is added, it is preferable that the V content be 0.1% or less, more preferably 0.04% to 0.08%.
  • Mg 0.0005% or more and 0.005% or less
  • Mg is a chemical element which is effective for improving toughness as a result of dispersion of oxides. It is preferable that the Mg content be at least 0.0005% or more in order to realize this effect, but the effect becomes saturated in the case where the Mg content is more than 0.005%. Therefore, in the case where Mg is added, it is preferable that the Mg content be 0.005% or less.
  • Zr is a chemical element which is effective for improving toughness as a result of dispersion of oxides. It is preferable that the Zr content be at least 0.003% or more in order to realize this effect, but the effect becomes saturated in the case where the Zr content is more than 0.02%. Therefore, in the case where Zr is added, it is preferable that the Zr content be 0.02% or less, more preferably 0.004% to 0.018%.
  • the REM is a chemical element which is effective for improving toughness as a result of the dispersion of oxides. It is preferable that the REM content be at least 0.003% or more in order to realize this effect, but the effect becomes saturated in the case where the REM content is more than 0.02%. Therefore, in the case where REM is added, it is preferable that the REM content be 0.02% or less, more preferably 0.004% to 0.018%.
  • O is contained as an inevitable impurity and decreases cleanliness as a result of being present in the form of oxides in steel. Therefore, it is preferable that the O content be as small as possible in the present invention. In the case where the O content is more than 0.0030%, since there is an increase in the size of CaO containing inclusions, there is a negative effect on toughness. Furthermore, in order to crystallize Ca in the form of CaS in the present invention, since O has strong affinity for Ca, it is preferable that the O content in molten steel be decreased to 0.0030% or less by performing intensive degassing or by adding a deoxidation agent before Ca is added. 0.3 ⁇ ACR ⁇ 0.8
  • ACR (Ca - (0.18 + 130xCa) ⁇ O)/1.25/S, where Ca, O and S respectively represent the contents (mass%) of Ca, O and S.
  • ACR value By controlling ACR value to be 0.3 or more and 0.8 or less, since MnS, which is effective as a nucleus of ferrite formation, is precipitated on CaS and finely dispersed, it is possible to realize an increase in toughness by forming a fine (ferrite + pearlite) structure in a welded heat affected zone when high-heat input welding is performed.
  • a steel slab which is used as a raw material of the tapered plate according to the present invention may be manufactured by smelting steel having the chemical composition described above using an ordinary refining process such as a steel converter, an electric furnace or a vacuum melting furnace and then by casting the smelted steel using an ordinary method such as a continuous casting method or an ingot casting-slabbing rolling method, and there is no particular limitations on what methods are used.
  • a slab heating temperature, hot rolling conditions and cooling conditions are specified as described hereafter.
  • Slab heating temperature 1000°C or higher and 1200°C or lower
  • the slab heating temperature is set to the range of 1000°C or higher and 1200°C or lower, preferably to the range of 1030°C to 1180°C.
  • hot rolling After a steel slab has been heated, hot rolling is performed.
  • a taper in which a plate thickness changes in the longitudinal direction is provided. Change in plate thickness in the longitudinal direction of a tapered plate is achieved by changing a roll gap while hot rolling in a predetermined pass after starting rolling of the steel plate.
  • the finishing rolling temperature of hot rolling is set to be 900°C or lower and equal to or higher than the Ar 3 point in terms of the surface temperature of a steel plate.
  • the finishing rolling temperature is set to be 900°C or lower and equal to or higher than the Ar 3 point, preferably to the range of (Ar 3 point + 10°C) to 880°C.
  • accelerated cooling is performed.
  • a cooling stop temperature is higher than 500°C, since it is impossible to obtain a steel plate having a tensile strength of 570 MPa or more, accelerated cooling is performed until the surface temperature of a steel plate decreases to a temperature of 500°C or lower, preferably to the range of 490°C or lower.
  • the surface temperature of a steel plate which is used to specify the hot rolling conditions and cooling conditions, can be determined using, for example, a radiation thermometer.
  • a tapered plate having a tensile strength of 570 MPa or more and excellent toughness of a welded heat-affected zone formed as a result of performing high-heat input welding despite that a difference in thickness (taper amount) between a thicker portion and a thinner portion of the tapered plate is 10 mm or more in the steel plate.
  • tapered plates having a thickness of the thicker portion of 60 mm, a thickness of the thinner portion of 50 mm and a taper amount (difference in thickness between the thicker portion and the thinner portion) of 10 mm, were manufactured.
  • Specimens described below were respectively cut out from a depth of 1/4 of the plate thickness of a thicker portion and a thinner portion of the tapered plate.
  • Round bar type tensile specimens having a parallel part of 14 ⁇ ⁇ 85 mm and a gauge length of 70 mm were cut out in a direction perpendicular to the rolling direction, and 2 mm V notched Charpy specimens were cut out in a direction parallel to the rolling direction.
  • the absorbed energy at - 40°C and strength of a base metal were evaluated.
  • the absorbed energy at -40°C was defined by an average value for three specimens.
  • HAZ welded heat affected zone
  • This weld thermal cycle includes a cooling step that decreases the temperature of the test pieces, which have been heated to 1450°C, from 800°C to 500°C in 270 seconds (This cycle corresponds to a thermal cycle in which a welded heat affected zone undergoes when a steel plate having a plate thickness of 55 mm is subjected to electrogas arc welding with a heat input of 400 kJ/cm).
  • tapered plates having a thickness of the thicker portion of 60 mm, a thickness of the thinner portion of 50 mm and a taper amount (difference in thickness between the thicker portion and the thinner portion) of 10 mm, were manufactured.
  • Specimens described below were respectively cut out from a depth of 1/4 of the plate thickness of a thicker portion and a thinner portion of the tapered plate.
  • Round bar type tensile specimens having a parallel part of 14 ⁇ ⁇ 85 mm and a gauge length of 70 mm were cut out in a direction perpendicular to the rolling direction, and 2 mm V notched Charpy specimens were cut out in a direction parallel to the rolling direction.
  • the absorbed energy at - 40°C and strength of a base metal were evaluated.
  • the absorbed energy at -40°C was defined by an average value of three specimens.
  • HAZ welded heat affected zone
  • This weld thermal cycle includes a cooling step that decreases the temperature of the test pieces, which have been heated to 1450°C, from 800°C to 500°C in 270 seconds (This cycle corresponds to a thermal cycle in which a welded heat affected zone undergoes when a steel plate having a plate thickness of 55 mm is subjected to electrogas arc welding with a heat input of 400 kJ/cm).
  • Table 1-1 (mass%) Steel No. C Si Mn P S Al Cu Ni Cr Mo V Nb Ti Ca Classification 1 0.055 0.06 2.05 0.005 0.0022 0.048 - - - - - 0.013 0.017 0.0022
  • Example 2 0.100 0.25 1.53 0.011 0.0019 0.032 - - - - - 0.012 0.013 0.0025
  • Example 3 0.058 0.07 1.
  • Example 4 0.051 0.17 1.82 0.004 0.0019 0.036 - - 0.12 - - 0.010 0.013 0.0018
  • Example 5 0.049 0.10 1.98 0.005 0.0021 0.055 - - 0.20 - - 0.011 0.011 0.0017
  • Example 6 0.045 0.07 1.85 0.008 0.0010 0.042 - - - 0.2 - 0.012 0.014 0.0031
  • Example 7 0.042 0.12 1.52 0.006 0.0021 0.036 0.45 0.78 - - 0.04 0.007 0.011 0.0016
  • Example 8 0.072 0.08 1.56 0.007 0.0035 0.055 0.38 0.87 - - - 0.008 0.008 0.0021
  • Example 9 0.170 0.07 1.82 0.006 0.0023 0.042 - - - - 0.012 0.013 0.0015 Comparative Example 10

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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (4)

  1. Procédé de fabrication d'une plaque effilée présentant une résistance à la traction de 570 MPa ou plus et une différence d'épaisseur entre une partie plus épaisse et une partie plus fine de 10 mm ou plus, le procédé comprenant le chauffage à une température de 1000 °C ou plus et 1200 °C ou moins, d'une brame d'acier présentant une composition chimique consistant en, en % en masse :
    C : 0,03 % ou plus et 0,12 % ou moins
    Si : 0,03 % ou plus et 0,5 % ou moins
    Mn : 0,8 % ou plus et 2,2 % ou moins
    P : 0,015 % ou moins
    S : 0,0005 % ou plus et 0,0050 % ou moins
    Al : 0,005 % ou plus et 0,1 % ou moins
    Nb : 0,003 % ou plus et 0,014 % ou moins
    Ti : 0,003 % ou plus et 0,02 % ou moins
    B : 0,0003 % ou plus et 0,0025 % ou moins
    N : 0,0030 % ou plus et 0,0070 % ou moins
    Ca : 0,0005 % ou plus et 0,0050 % ou moins,
    facultativement un, deux ou plus de deux sélectionnés parmi
    Cu : 0,05 % ou plus et 1,0 % ou moins
    Ni : 0,05 % ou plus et 1,0 % ou moins
    Cr : 0,05 % ou plus et 0,5 % ou moins
    Mo : 0,05 % ou plus et 0,5 % ou moins, et
    V : 0,02 % ou plus et 0,1 % ou moins,
    facultativement un, deux ou plus de deux sélectionnés parmi
    Mg : 0,0005 % ou plus et 0,005 % ou moins
    Zr : 0,003 % ou plus et 0,02 % ou moins, et
    REM : 0,003 % ou plus et 0,02 % ou moins
    et facultativement O: 0,0030 % ou moins, le reste étant Fe et les impuretés inévitables,
    dans laquelle l'expression (1) est satisfaite, par la mise en oeuvre d'un laminage à chaud sur la brame chauffée dans lequel l'épaisseur de la plaque change dans la direction longitudinale afin de former une forme effilée à une température de laminage de finition de 900 °C ou moins et supérieure ou égale au point Ar3 et ensuite par la mise en oeuvre d'un refroidissement accéléré sur la plaque d'acier laminée à chaud jusqu'à une température de 500 °C ou moins : 0 ≤ N − Ti / 3,42 ≤ 0,0025
    Figure imgb0011
     où N et Ti représentent respectivement les teneurs (% en masse) de N et Ti.
  2. Procédé de fabrication d'une plaque effilée présentant une résistance à la traction de 570 MPa ou plus et une différence d'épaisseur entre une partie plus épaisse et une partie plus fine de 10 mm ou plus selon la revendication 1, la brame d'acier présentant une composition chimique contenant, en % en masse, un, deux ou plus de deux sélectionnés parmi :
    Cu : 0,05 % ou plus et 1,0 % ou moins
    Ni : 0,05 % ou plus et 1,0 % ou moins
    Cr : 0,05 % ou plus et 0,5 % ou moins
    Mo : 0,05 % ou plus et 0,5 % ou moins, et
    V : 0,02 % ou plus et 0,1 % ou moins.
  3. Procédé de fabrication d'une plaque effilée présentant une résistance à la traction de 570 MPa ou plus et une différence d'épaisseur entre une partie plus épaisse et une partie plus fine de 10 mm ou plus selon la revendication 1 ou 2, la brame d'acier présentant une composition chimique contenant, en % en masse, un, deux ou plus de deux sélectionnés parmi :
    Mg : 0,0005 % ou plus et 0,005 % ou moins
    Zr : 0,003 % ou plus et 0,02 % ou moins, et
    REM : 0,003 % ou plus et 0,02 % ou moins.
  4. Procédé de fabrication d'une plaque effilée présentant une résistance à la traction de 570 MPa ou plus et une différence d'épaisseur entre une partie plus épaisse et une partie plus fine de 10 mm ou plus selon l'une quelconque des revendications 1 à 3, la brame d'acier présentant une composition chimique contenant, en % en masse :
    O : 0,0030 % ou moins,
    dans lequel les teneurs en Ca, O et S satisfont l'expression (2) ci-dessous : 0,3 ≤ ACR ≤ 0,8
    Figure imgb0012
     où ACR = (Ca - (0,18 + 130×Ca)×O)/1,25/S, et où Ca, O et S représentent respectivement les teneurs (% en masse) de Ca, O et S.
EP12865903.4A 2012-01-18 2012-04-19 Procédé de production de plaque conique Not-in-force EP2806042B1 (fr)

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PCT/JP2012/061156 WO2013108419A1 (fr) 2012-01-18 2012-04-19 Procédé de production de plaque conique

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CN108396241B (zh) * 2017-02-08 2019-09-20 鞍钢股份有限公司 一种420MPa级LP钢板及其生产方法
CN108396222B (zh) * 2017-02-08 2019-09-20 鞍钢股份有限公司 一种235MPa级LP钢板及其生产方法
CN108396252B (zh) * 2017-02-08 2020-01-07 鞍钢股份有限公司 一种390MPa级LP钢板及其生产方法
CN108396245B (zh) * 2017-02-08 2019-12-13 鞍钢股份有限公司 一种345MPa级LP钢板及其生产方法
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WO2013108419A1 (fr) 2013-07-25
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