WO2013108419A1 - Procédé de production de plaque conique - Google Patents

Procédé de production de plaque conique Download PDF

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Publication number
WO2013108419A1
WO2013108419A1 PCT/JP2012/061156 JP2012061156W WO2013108419A1 WO 2013108419 A1 WO2013108419 A1 WO 2013108419A1 JP 2012061156 W JP2012061156 W JP 2012061156W WO 2013108419 A1 WO2013108419 A1 WO 2013108419A1
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Prior art keywords
thickness
plate
toughness
strength
less
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PCT/JP2012/061156
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English (en)
Japanese (ja)
Inventor
横田　智之
雅美 中村
長谷　和邦
三田尾　眞司
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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
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to KR1020147022106A priority Critical patent/KR101612660B1/ko
Priority to CN201280067544.9A priority patent/CN104066858B/zh
Priority to EP12865903.4A priority patent/EP2806042B1/fr
Publication of WO2013108419A1 publication Critical patent/WO2013108419A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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 is suitable for shipbuilding, architecture, and the like, and is a tapered plate (tapered plate plates), an LP steel plate (Longitudinally Profiled) whose thickness changes continuously in the longitudinal direction. (Also referred to as Steel Plate)), high-heat input welding with a small difference in strength in the steel sheet and a welding heat input exceeding 300 kJ / cm is applicable.
  • the shape of the thick steel plate is generally uniform in both the width direction and the longitudinal direction. However, when the plate thickness is continuously changed in the longitudinal direction, it may have a great effect on reduction of material weight and reduction of welding man-hour.
  • a thick steel plate is called a tapered plate, a tapered steel plate, an LP steel plate, or the like, and there are many proposals such as Patent Document 1, Patent Document 2, and Patent Document 3 for its manufacturing method. These proposals are aimed at how to produce a taper plate with high dimensional accuracy.
  • the material properties (material properties) and material uniformity (material uniformity) of the steel sheet cannot be put into practical use unless they are satisfied.
  • TMCP Thermo-Mechanical Control Process
  • austenite non-recrystallization region austenite + ferrite
  • austenite + ferrite austenite + ferrite
  • the ferrite grains are made finer and further cooled as necessary to further increase the strength and toughness.
  • the controlled rolling is strong processing at a low temperature such as austenite non-recrystallized zone rolling or (austenite + ferrite) two-phase zone rolling (dual phase rolling, dual-phase rolling)
  • the thickness direction as in the taper plate When the wall thickness is different, the temperature difference between the steel plate temperature between the thin part and the thick part becomes too large, and the difference in strength remains.
  • Patent Document 4 in order to obtain a uniform material, the temperature in the longitudinal direction before cooling is measured, and based on this measured value, the optimum cooling condition (optimum cooling condition) of each point is calculated, A taper plate cooling method is shown in which the feeding speed during cooling is corrected according to the thickness.
  • Patent Document 5 the cooling is started at the thin part and the thick part of the steel sheet at the same time, and the taper plate cooling method for changing the timing of exiting the cooling device, or the cooling is started sequentially in the longitudinal direction of the steel sheet, and the cooling is finished simultaneously.
  • a taper plate cooling method is shown. Both are proposals to reduce the variation in material properties in the steel sheet when accelerated cooling is performed.
  • Patent Document 6 is an example of trying to solve such a problem by devising the component composition of the steel sheet.
  • the variation in strength can be reduced by increasing the Nb addition amount to 0.015% to 0.06%.
  • Hv 20-50 value represented by Hv 20-50 ⁇ 110 + 460C + 44Si + 39Mn ⁇ 31Cu ⁇ 9Ni + 11Cr + 22Mo + 180V + 9600B ⁇ 23000Mo ⁇ B It is disclosed that variation in strength can be reduced if the difference in Hv hardness when cooling to room temperature at a cooling rate corresponding to cooling is 15 or less.
  • Japanese Patent Publication No. 50-36826 Japanese Patent Publication No. 60-124 Japanese Patent Publication No. 5-49361 JP-A-62-166013 JP 7-68309 A Japanese Patent No. 3180944 Japanese Patent No. 3972553
  • the present invention advantageously solves the above-mentioned problems, and has a tensile strength of 570 MPa or more, small variations in strength, and a welding heat input with a large heat input exceeding 300 kJ / cm.
  • An object of the present invention is to provide a method for producing a taper plate having a superior difference in toughness of the part and having a difference (taper amount) between a thick part thickness and a thin part thickness in the longitudinal direction of 10 mm or more.
  • the present inventors investigated the influence of Ti and N contents on the strength difference between the thick part and thin part of B-containing taper plates having different Ti and N contents, and Ti and N contents.
  • Ti and N contents when 0 ⁇ N-Ti / 3.42 ⁇ 0.0025 is satisfied, an appropriate amount of solid solution B can be stably secured, and the strength difference between the thick part and the thin part is small. I got the knowledge that
  • the present invention has been made by further study based on the above knowledge, that is, the present invention, 1. % By mass C: 0.03-0.12% Si: 0.03-0.5% Mn: 0.8 to 2.2% P: 0.015% or less S: 0.0005 to 0.0050% Al: 0.005 to 0.1% Nb: 0.003 to 0.014% Ti: 0.003-0.02% B: 0.0003 to 0.0025% N: 0.0030 to 0.0070% Ca: 0.0005 to 0.0050% And satisfies the formula (1), After the steel slab composed of the remaining Fe and inevitable impurities is heated to 1000 ° C.
  • the component composition of the steel slab is further mass%, Cu: 0.05 to 1.0% Ni: 0.05 to 1.0% Cr: 0.05 to 0.5% Mo: 0.05 to 0.5% V: 0.02 to 0.1% 1 or 2 or more types selected from above,
  • composition of the steel slab is further mass%, Mg: 0.0005 to 0.005% Zr: 0.003 to 0.02% REM: 0.003-0.02% 1 or 2 or more types selected from among the above, the production of a taper plate having a tensile strength of 570 MPa or more and a difference between the thickness of the thick part and the thickness of the thin part of 10 mm or more Method. 4).
  • the component composition of the steel slab further includes 0: 0.0030% or less in terms of mass%, and each content of Ca, O, and S satisfies the following formula (2).
  • ACR (Ca ⁇ (0.18 + 130 ⁇ Ca) ⁇ O) /1.25/S Ca, O, and S represent the content (% by mass) of each component.
  • the tensile strength is 570 MPa or more, and the difference in strength between the thick part and the thin part is small, such as submerged arc welding, electrogas welding, electroslag welding.
  • a component composition and manufacturing conditions are prescribed
  • % is mass%.
  • the toughness of the welded heat affected zone is lowered, so 0.03% to 0.12%.
  • the content is 0.04 to 0.09%.
  • Si 0.03-0.5% Si is added in an amount of 0.03% or more in order to ensure deoxidation and strength. If added over 0.5%, in the case of high heat input welding, island martensite is generated in the weld heat affected zone and the toughness is deteriorated, so the content is made 0.5% or less. Preferably it is 0.4% or less.
  • Mn 0.8 to 2.2% Mn is added in an amount of 0.8% or more in order to ensure the strength of the base material. On the other hand, if it exceeds 2.2%, the toughness of the welded portion is remarkably deteriorated, so 0.8 to 2.1%, more preferably 1.2 to 2.0%.
  • P 0.015% or less
  • P is an unavoidable impurity in the present invention.
  • an island martensite (MA-A constituent) is formed in the heat-affected zone by high heat input welding.
  • CTOD characteristics rack tip opening displacement property.
  • it is 0.012% or less.
  • S 0.0005 to 0.0050% S is made to be 0.0005% or more in order to generate CaS and MnS. On the other hand, if it exceeds 0.0050%, the toughness of the base material is lowered, so 0.0005 to 0.0050% is set.
  • Al 0.005 to 0.1% Al is made 0.005% or more in order to deoxidize steel. On the other hand, if it exceeds 0.1%, the toughness of the base metal is lowered and the toughness of the weld metal is also lowered, so 0.005 to 0.1%, preferably 0.01 to 0.06%. To do.
  • Nb 0.003 to 0.014%
  • Nb is effective to ensure the strength, toughness of the base metal and the strength of the welded joint (strength of weld joint).
  • Nb is required to be 0.003% or more, but exceeds 0.014%.
  • the toughness of the weld heat affected zone decreases, so 0.003 to 0.014%.
  • the content is 0.005 to 0.013%.
  • Ti 0.003-0.02% Ti forms and precipitates TiN during solidification, suppresses the coarsening of austenite grains in the weld heat affected zone, precipitates ferrite by forming ferrite transformation nuclei (nucleus of ferrite transformation), and toughness In order to improve this, 0.003% or more is added. On the other hand, if it exceeds 0.02%, the TiN particles become coarse and the toughness is lowered, so 0.003 to 0.02%. Preferably, the content is 0.005 to 0.018%.
  • B 0.0003 to 0.0025% B contributes to hardenability as solid solution B (solid B) during steel plate production and improves the base metal strength.
  • solid B solid solution B
  • BN is generated in the heat affected zone.
  • 0.0003% or more is added.
  • the content is 0.005 to 0.0022%.
  • N 0.0030 to 0.0070% N generates 0.0030% or more in order to generate TiN effective for improving toughness.
  • solid solution B that contributes to hardenability may not be ensured during steel sheet production, and TiN in the vicinity of the bond bond is dissolved when high heat input welding is performed.
  • the content is made 0.0030 to 0.0070%.
  • Ca 0.0005 to 0.0050% Ca makes the toughness of the weld heat-affected zone good when large heat input welding is performed. MnS, TiN, BN precipitates on CaS, and increases the frequency of ferrite nucleation. Improve toughness.
  • the content is made 0.0005% or more.
  • 0.0005 to 0.0050% the effect is saturated, so 0.0005 to 0.0050% is set.
  • it is 0.0005 to 0.0030%, more preferably 0.0007 to 0.0030%.
  • Cu 0.05 to 1.0% Cu is effective in increasing the strength of the base material, and it is preferable to contain 0.05% or more in order to obtain the effect. However, if it exceeds 1.0%, hot shortness occurs, and the steel plate When it contains, it is preferable to set it as 1.0% or less. More preferably, the content is 0.1 to 0.8%.
  • Ni 0.05 to 1.0% Ni increases the strength while maintaining the base material with high toughness, so it is preferable to contain 0.05% or more in order to obtain the effect. On the other hand, if it exceeds 1.0%, the effect is saturated, so when it is contained, it is preferably 0.05 to 1.0%. More preferably, the content is 0.1 to 0.9%.
  • 0.05 to 0.5% Cr is effective for increasing the strength of the base material, and is preferably contained in an amount of 0.05% or more in order to obtain the effect. However, when added in a large amount, the toughness is deteriorated. It is preferable to set it to 5% or less. More preferably, the content is 0.1 to 0.4%.
  • Mo 0.05 to 0.5% Mo is effective for increasing the strength of the base material and is preferably contained in an amount of 0.05% or more in order to obtain the effect. However, if added in a large amount, the toughness deteriorates. It is preferable to set it to 5% or less. More preferably, the content is 0.07 to 0.4%.
  • V 0.02 to 0.1%
  • V is effective for increasing the strength of the base material, and is preferably contained in an amount of 0.02% or more in order to obtain the effect. However, if it exceeds 0.1%, the toughness will be lowered. Is preferably 0.1% or less. More preferably, the content is 0.04 to 0.08%.
  • Mg 0.0005 to 0.005%
  • Mg is an element having an effect of improving toughness due to dispersion of oxides. In order to exert such an effect, it is preferable to contain at least 0.0005% or more, but even if it contains more than 0.005%, the effect is saturated. It is preferable to do.
  • Zr 0.003 to 0.02%
  • Zr is an element having an effect of improving toughness due to oxide dispersion. In order to exert such an effect, it is preferable to contain at least 0.003% or more, but even if it exceeds 0.02%, the effect is saturated. It is preferable to do. More preferably, the content is 0.004 to 0.018%.
  • REM 0.003-0.02% REM is an element having an effect of improving toughness due to dispersion of oxides. In order to exert such an effect, it is preferable to contain at least 0.003% or more, but even if it exceeds 0.02%, the effect is saturated. It is preferable to do. More preferably, the content is 0.004 to 0.018%. O: 0.0030% or less O is contained as an unavoidable impurity, and exists as an oxide in the steel, which reduces cleanliness. For this reason, it is preferable to reduce as much as possible in the present invention. If the O content exceeds 0.0030%, CaO-based inclusions become coarse and adversely affect toughness.
  • This MnS is elongated by rolling at the time of manufacturing the steel sheet to cause a decrease in the toughness of the base material, and MnS melts in the weld heat affected zone which is the main point of the present invention, so that fine dispersion is not achieved.
  • ACR exceeds 0.8
  • most of S is fixed by Ca, and MnS acting as a ferrite formation nucleus does not precipitate on CaS, so that a sufficient function is not exhibited.
  • the steel slab used as the material of the taper plate of the present invention is made of steel having the above-described composition, for example, a normal converter such as a converter, an electric furnace, a vacuum melting furnace, or the like. After being melted by a refining process, it can be produced by a conventional method such as continuous casting or ingot-bundling rolling, and there is no particular limitation.
  • a normal converter such as a converter, an electric furnace, a vacuum melting furnace, or the like.
  • slab heating temperature slab heating temperature
  • hot rolling conditions hot rolling conditions
  • cooling conditions cooling conditions
  • the slab heating temperature 1000 ⁇ 1200 °C
  • the additive components are not sufficiently dissolved.
  • the temperature exceeds 1200 ° C.
  • the austenite grains become coarse, and even after rolling, the fineness does not advance and the toughness deteriorates.
  • the slab heating temperature is in the range of 1000 to 1200 ° C.
  • the temperature is preferably in the range of 1030 to 1180 ° C.
  • Hot rolling conditions After the steel slab is heated, hot rolling is performed.
  • tapers with different plate thicknesses are provided in the longitudinal direction.
  • the change in the plate thickness in the longitudinal direction of the taper plate can be achieved by biting the steel plate and then hot rolling by changing the roll opening in a predetermined pass.
  • the rolling reduction (also referred to as the rolling reduction) for each pass is not particularly limited.
  • the rolling rolling temperature of hot rolling is 900 ° C. or less and Ar 3 points or more at the steel sheet surface temperature. If the finishing temperature is less than 3 points of Ar, a predetermined strength cannot be obtained, and if it exceeds 900 ° C., the toughness deteriorates, so the finishing temperature is 900 ° C. or less and Ar 3 points or more. Preferably, it is in the range of (Ar 3 + 10 ° C.) to 880 ° C.
  • Cooling conditions After the hot rolling is completed, accelerated cooling is performed. If the cooling stop temperature exceeds 500 ° C., steel sheet strength with a tensile strength of 570 MPa or higher cannot be obtained, and therefore, accelerated cooling is performed to a steel sheet surface temperature of 500 ° C. or lower. Preferably it is set as the range of 490 degrees C or less.
  • regulates hot rolling conditions and cooling conditions can be measured using a radiation thermometer (radiation thermometer), for example.
  • a radiation thermometer radiation thermometer
  • an appropriate amount of solid solution B can be stably secured by the combination of the above-described component composition and production conditions, and the effect of improving the hardenability and the effect of improving the toughness of the weld heat affected zone of high heat input welding. Therefore, even if the difference between the thick part thickness and the thin part thickness (taper amount) of the taper plate is 10 mm or more in the steel plate, the toughness of the weld heat affected zone of the high heat input welding excellent in the tensile strength of 570 MPa or more.
  • a steel slab having the chemical composition shown in Table 1 is hot-rolled under the conditions shown in Table 2, and a thick part 60 mm, a thin part 50 mm, and a taper amount (difference between the thick part thickness and the thin part thickness) 10 mm.
  • the taper plate was manufactured.
  • a round bar tensile test piece with a parallel part of 14 ⁇ x 85mm and a gauge length of 70mm is rolled in the rolling direction ( In the direction perpendicular to the rolling direction, a 2 mm V notch charpy specimen was taken in a direction parallel to the rolling direction, and the strength of the base material and the absorbed energy (absorbed energy) at ⁇ 40 ° C. were evaluated.
  • the absorbed energy at ⁇ 40 ° C. was an average value of three values.
  • HAZ weld heat-affected zone
  • specimens having a width of 80 mm, a length of 80 mm, and a thickness of 15 mm were collected from these steel plates for a welding thermal cycle.
  • 800-500 ° C. was cooled at 270 s (corresponding to the heat cycle of the weld heat-affected zone with heat input of 400 kJ / cm in electrogas welding on a steel plate having a thickness of 55 mm).
  • a 2 mm V notch Charpy test was performed on the piece to evaluate reproducible HAZ toughness (toughness of Simulated HAZ).
  • Table 2 shows the mechanical properties of the thick and thin taper plates and the toughness after the heat cycle.
  • 1-No. No. 8 satisfies YS: 460 MPa or more, TS: 570 MPa or more, absorbed energy at ⁇ 40 ° C .: 300 J or more (average of three), and the strength difference between the thick part and the thin part is less than 20 MPa for TS, YS Is less than 30 MPa, and the reproduced HAZ toughness is excellent at vTrs: ⁇ 40 ° C. or lower.
  • N-Ti / 3.42> 0.0025 No. 11 no. No. 14 has a large strength difference between the thick part and the thin part.
  • those that are outside the proper components or manufacturing conditions cannot satisfy any one or more of YS: 460 MPa or more, TS: 570 MPa or more, absorbed energy: 300 J or more, and reproduced HAZ toughness vTrs: ⁇ 40 ° C. or less. It is the result.
  • a steel slab having the chemical composition shown in Table 3 is hot-rolled under the conditions shown in Table 4, and a taper plate having a thickness of 60 mm, a thickness of 50 mm, and a taper amount (difference between the thickness of the thickness and the thickness of the thin part) of 10 mm is obtained. Manufactured.
  • HAZ weld heat affected zone
  • a test piece having a width of 80 mm, a length of 80 mm and a thickness of 15 mm was taken from these steel sheets for heating and heat cycle and heated to 1450 ° C. 2 mm V notch Charpy for a test piece provided with a welding heat cycle that is cooled to 270 s at 800 to 500 ° C. (corresponding to the heat cycle of the weld heat-affected zone with a heat input of 400 kJ / cm in electrogas welding on a steel sheet having a thickness of 55 mm). Tests were performed to evaluate reproducible HAZ toughness.
  • Table 4 shows the mechanical properties of the thick and thin portions of the taper plate and the toughness after the welding heat cycle.
  • No. of the present invention example satisfying the ACR regulations. 21 and no. No. 22 satisfies YS: 460 MPa or more, TS: 570 MPa or more, absorbed energy at ⁇ 40 ° C .: 300 J or more (average of three), and the strength difference between the thick part and the thin part is less than 20 MPa for TS, YS Is less than 30 MPa, and the reproduced HAZ toughness is excellent at vTrs: ⁇ 65 ° C. or less.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
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Abstract

La présente invention concerne un procédé de production d'une plaque conique permettant de mettre en œuvre un soudage avec apport de chaleur élevé à savoir un apport de chaleur de soudage dépassant 300 kJ/cm. De plus, la plaque conique selon l'invention présente une résistance à la traction supérieure ou égale à 570 MPa. Plus particulièrement, le procédé selon l'invention comprend les étapes consistant à : chauffer une brame d'acier contenant, en % en masse, de 0,03 à 0,12 % de C, de 0,03 à 0,5 % de Si, de 0,8 à 2,2 % de Mn, au plus 0,015 % de P, de 0,0005 à 0,0050 % de S, de 0,005 à 0,1 % d'Al, de 0,003 à 0,014 % de Nb, de 0,003 à 0,02 % de Ti, de 0,0003 à 0,0025 % de B, de 0,0030 à 0,0070 % de N et de 0,0005 à 0,005 % de Ca, le reste consistant en du Fe et des impuretés inévitables et satisfaisant à la relation (1) à une température située dans la plage allant de 1 000 à 1 200 °C; soumettre la brame résultante à un laminage à chaud, la température finale de laminage étant située dans la plage allant de la température Ar3 à la température de 900 °C pour convertir la brame en une plaque conique dont l'épaisseur de plaque diminue longitudinalement; et soumettre ensuite la plaque conique à un refroidissement accéléré afin d'abaisser la température de la plaque conique à une température inférieure ou égale à 500 °C. 0 ≤ N - Ti / 3,42 ≤ 0,0025 [dans laquelle N et Ti représentent respectivement les teneurs (% en masse) de ces éléments] ··· (1)
PCT/JP2012/061156 2012-01-18 2012-04-19 Procédé de production de plaque conique Ceased WO2013108419A1 (fr)

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KR1020147022106A KR101612660B1 (ko) 2012-01-18 2012-04-19 테이퍼 플레이트의 제조 방법
CN201280067544.9A CN104066858B (zh) 2012-01-18 2012-04-19 楔形板材的制造方法
EP12865903.4A EP2806042B1 (fr) 2012-01-18 2012-04-19 Procédé de production de plaque conique

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JP2012-007765 2012-01-18
JP2012007765A JP5772620B2 (ja) 2011-01-18 2012-01-18 テーパプレートの製造方法

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WO2016060141A1 (fr) * 2014-10-17 2016-04-21 Ｊｆｅスチール株式会社 Acier pour soudage à haute énergie

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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
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
KR20190076205A (ko) 2017-12-22 2019-07-02 동국제강주식회사 변단면을 가지는 후판 제조 방법
CN111996462B (zh) * 2020-09-07 2022-02-18 鞍钢股份有限公司 一种纵向变厚度超高强船板及生产方法
CN116770190B (zh) * 2023-05-30 2024-05-14 鞍钢股份有限公司 一种低屈强比纵向变厚度桥梁用钢及其制造方法

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EP2806042A4 (fr) 2015-06-03
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CN104066858A (zh) 2014-09-24
CN104066858B (zh) 2015-11-25
KR20140110065A (ko) 2014-09-16
EP2806042B1 (fr) 2018-09-12

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