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WO2020067210A1 - 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管 - Google Patents

耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管 Download PDF

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WO2020067210A1
WO2020067210A1 PCT/JP2019/037698 JP2019037698W WO2020067210A1 WO 2020067210 A1 WO2020067210 A1 WO 2020067210A1 JP 2019037698 W JP2019037698 W JP 2019037698W WO 2020067210 A1 WO2020067210 A1 WO 2020067210A1
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Prior art keywords
steel sheet
temperature
less
sour
strength
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PCT/JP2019/037698
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English (en)
French (fr)
Japanese (ja)
Inventor
純二 嶋村
横田　智之
上岡　悟史
石川　信行
Original Assignee
Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to EP19864846.1A priority Critical patent/EP3859026B1/en
Priority to BR112021005599-1A priority patent/BR112021005599B1/pt
Priority to JP2020524425A priority patent/JP6825749B2/ja
Priority to RU2021112075A priority patent/RU2767261C1/ru
Priority to KR1020217011928A priority patent/KR102524176B1/ko
Priority to CN201980063051.XA priority patent/CN112752858B/zh
Publication of WO2020067210A1 publication Critical patent/WO2020067210A1/ja

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    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
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    • C21D6/00—Heat treatment of ferrous alloys
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    • 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
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a high-strength steel plate for a sour-resistant line pipe excellent in material uniformity in a steel plate, which is suitable for use in a line pipe in the fields of construction, marine structures, shipbuilding, civil engineering, and construction industrial machinery, and its production. It is about the method.
  • the present invention also relates to a high-strength steel pipe using the above-mentioned high-strength steel plate for a sour resistant line pipe.
  • a line pipe is manufactured by forming a steel plate manufactured by a thick plate mill or a hot rolling mill into a steel pipe by UOE forming, press bend forming, roll forming, or the like.
  • line pipes used for transporting crude oil and natural gas containing hydrogen sulfide are resistant to hydrogen-induced cracking (HIC (Hydrogen Induced Cracking)) and sulfides.
  • HIC Hydro-induced cracking
  • So-called sour resistance such as stress corrosion cracking resistance (SSCC (Sulfide Stress Corrosion Cracking) resistance) is required.
  • SSCC Stress corrosion cracking resistance
  • HIC absorbs hydrogen ions due to the corrosion reaction on the surface of the steel material, penetrates into the steel as atomic hydrogen, and diffuses and accumulates around the non-metallic inclusions such as MnS and the hard second phase structure in the steel. Therefore, it becomes molecular hydrogen, and cracks occur due to its internal pressure.
  • TMCP Thermo-Mechanical Control Process
  • the surface layer of the steel sheet is rapidly cooled, so that the hardness of the surface layer becomes higher than that inside the steel sheet, and the hardness distribution in the sheet thickness direction varies. Therefore, there is a problem from the viewpoint of ensuring material uniformity in the steel sheet.
  • Patent Documents 1 and 2 after rolling, by performing controlled cooling at a high cooling rate to reheat the surface before the surface layer completes the bainite transformation, in the thickness direction A method for producing a steel sheet having a small material difference is disclosed.
  • Patent Documents 3 and 4 disclose a method of manufacturing a steel sheet for line pipes, in which the surface of a steel sheet after accelerated cooling is heated to a higher temperature from the inside by using a high-frequency induction heating device to reduce the hardness of a surface layer portion. Have been.
  • Patent Documents 5 and 6 disclose methods of performing descaling immediately before cooling to reduce cooling unevenness caused by unevenness in scale thickness and improve the shape of a steel sheet.
  • the descaling reduces the surface property defect due to the indentation flaw of the scale at the time of hot straightening, and reduces the variation of the cooling stop temperature of the steel sheet to improve the steel sheet shape.
  • no consideration is given to cooling conditions for obtaining a uniform material. This is because if the cooling rate of the steel sheet surface varies, the hardness of the steel sheet varies. In other words, if the cooling rate is low, a film of bubbles is generated between the steel sheet surface and the cooling water when the steel sheet surface cools, and the bubbles are separated from the surface by the cooling water before the film forms a film. Nucleate boiling occurs at the same time, causing variations in the cooling rate of the steel sheet surface. As a result, the hardness of the steel sheet surface varies. The techniques described in Patent Documents 5 and 6 do not consider this point.
  • Patent Documents 1 to 6 conditions for avoiding fine cracks such as Fischer in an environment where the partial pressure of hydrogen sulfide is relatively low were not clear.
  • the present invention provides a sour line pipe that is not only excellent in HIC resistance but also excellent in SSCC resistance in a more severe corrosive environment and SSCC resistance in an environment having a low hydrogen sulfide partial pressure of less than 1 bar. It is an object of the present invention to provide a high-strength steel sheet for use together with its advantageous production method. Another object of the present invention is to propose a high-strength steel pipe using the high-strength steel plate for a sour resistant line pipe.
  • the present inventors have repeated numerous experiments and studies on the composition of the steel material, the microstructure, and the manufacturing conditions in order to secure the SSCC resistance under a more severe corrosive environment.
  • the lower 0.25 mm steel structure into a bainite structure having a dislocation density of 1.0 ⁇ 10 14 to 7.0 ⁇ 10 14 (m ⁇ 2 )
  • an increase in hardness in the coating process after pipe forming is reduced.
  • the steel pipe can be suppressed, and as a result, the SSCC resistance of the steel pipe is improved. Furthermore, in order to realize such a steel structure, it is necessary to strictly control the cooling rate at 0.25 mm below the surface of the steel sheet, and succeeded in finding the condition.
  • the addition of Mo is effective in suppressing the initial crack initiation.
  • the addition of Ni is suppressed, as in Fisher. It has been found that it is effective for avoiding fine cracks. The present invention has been made based on this finding.
  • the gist configuration of the present invention is as follows. [1] In mass%, C: 0.02 to 0.08%, Si: 0.01 to 0.50%, Mn: 0.50 to 1.80%, P: 0.001 to 0.015% , S: 0.0002 to 0.0015%, Al: 0.01 to 0.08%, Mo: 0.01 to 0.50%, and Ca: 0.0005 to 0.005%.
  • Nb contains at least one selected from 0.005 to 0.1% and Ti: 0.005 to 0.1%, and the balance has a component composition of Fe and unavoidable impurities;
  • the steel structure at 0.25 mm below the surface of the steel sheet is a bainite structure having a dislocation density of 1.0 ⁇ 10 14 to 7.0 ⁇ 10 14 (m ⁇ 2 ),
  • the variation of Vickers hardness at 0.25 mm below the surface of the steel sheet is 30 HV or less at 3 ⁇ when the standard deviation is ⁇ ,
  • the variation of Vickers hardness in the thickness direction is 30 HV or less at 3 ⁇ when the standard deviation is ⁇
  • a high-strength steel plate for sour resistant line pipe having a tensile strength of 520 MPa or more.
  • the above-mentioned component composition further shows, by mass%, V: 0.005 to 0.1%, Zr: 0.0005 to 0.02%, Mg: 0.0005 to 0.02%, and REM: 0.
  • V 0.005 to 0.1%
  • Zr 0.0005 to 0.02%
  • Mg 0.0005 to 0.02%
  • REM 0.
  • a steel slab containing at least one selected from the group consisting of Nb: 0.005 to 0.1% and Ti: 0.005 to 0.1%, with the balance being Fe and unavoidable impurities, is 1000 to 1300 After heating to a temperature of °C, hot rolled into a steel sheet, Then, for the steel plate, Steel sheet surface temperature at the start of cooling: (Ar 3 -10 ° C.) or more, Average cooling rate from 750 ° C. to 550 ° C.
  • the above-mentioned component composition further shows, by mass%, V: 0.005 to 0.1%, Zr: 0.0005 to 0.02%, Mg: 0.0005 to 0.02%, and REM: 0.
  • the high-strength steel sheet for sour line pipe of the present invention and the high-strength steel pipe using the high-strength steel sheet for sour line pipe have not only HIC resistance but also SSCC resistance under severer corrosive environment and less than 1 bar. Also excellent in SSCC resistance in an environment with a low hydrogen sulfide partial pressure.
  • the method for producing a high-strength steel sheet for a sour line pipe of the present invention not only the HIC resistance but also the SSCC resistance under a more severe corrosive environment and the resistance under a low hydrogen sulfide partial pressure environment of less than 1 bar.
  • a high-strength steel plate for a sour-resistant line pipe having excellent SSCC properties can be manufactured.
  • C 0.02 to 0.08% C effectively contributes to the improvement of the strength, but if the content is less than 0.02%, sufficient strength cannot be ensured. On the other hand, if the content exceeds 0.08%, the hardness of the surface layer portion and the center segregation portion during accelerated cooling is reduced. , The SSCC resistance and the HIC resistance deteriorate. Further, the toughness also deteriorates. For this reason, the C content is limited to the range of 0.02 to 0.08%.
  • Si 0.01 to 0.50% Si is added for deoxidation, but if the content is less than 0.01%, the deoxidizing effect is not sufficient, and if it exceeds 0.50%, toughness and weldability are deteriorated. It is limited to the range of 01 to 0.50%.
  • Mn 0.50 to 1.80% Mn effectively contributes to the improvement of strength and toughness.
  • the content is less than 0.50%, the effect of adding Mn is poor.
  • the content exceeds 1.80%, the hardness of the surface layer portion and the center segregation portion during accelerated cooling is reduced. , The SSCC resistance and the HIC resistance deteriorate. In addition, weldability also deteriorates. Therefore, the amount of Mn is limited to the range of 0.50 to 1.80%.
  • P 0.001 to 0.015%
  • P is an unavoidable impurity element, and degrades the weldability and degrades the HIC resistance by increasing the hardness of the central segregation part. If it exceeds 0.015%, the tendency becomes remarkable, so the upper limit is set to 0.015%. Preferably it is 0.008% or less. The lower the content, the better, but from the viewpoint of refining cost, the content is set to 0.001% or more.
  • S 0.0002-0.0015%
  • S is an unavoidable impurity element, and is preferably small in steel because it becomes MnS inclusions and degrades HIC resistance, but is allowed up to 0.0015%.
  • Al 0.01 to 0.08% Al is added as a deoxidizing agent, but if it is less than 0.01%, there is no effect, whereas if it exceeds 0.08%, the cleanliness of the steel decreases and the toughness deteriorates. It is limited to the range of 01 to 0.08%.
  • Mo 0.01 to 0.50% Mo is an element effective in improving toughness and increasing strength, and is an element effective in improving SSCC resistance regardless of hydrogen sulfide partial pressure. To obtain this effect, it is necessary to contain 0.01% or more, and preferably 0.10% or more. On the other hand, if the content is too large, the quenchability becomes excessive, so that the dislocation density described later increases and the SSCC resistance deteriorates. In addition, weldability also deteriorates. Therefore, the amount of Mo is set to 0.50% or less, preferably 0.40% or less.
  • Ca 0.0005 to 0.005% Ca is an element effective for improving the HIC resistance by controlling the form of the sulfide-based inclusion, but if it is less than 0.0005%, the effect of its addition is not sufficient. On the other hand, when the content exceeds 0.005%, not only the effect is saturated, but also the HIC resistance is deteriorated due to a decrease in the cleanliness of the steel. Therefore, the Ca content is limited to the range of 0.0005 to 0.005%. .
  • Nb at least one selected from 0.005 to 0.1% and Ti: 0.005 to 0.1%
  • Nb and Ti are effective elements for increasing the strength and toughness of the steel sheet. . If the content of each element is less than 0.005%, the effect of the addition is poor, while if the content exceeds 0.1%, the toughness of the welded portion is deteriorated. Therefore, at least one of Nb and Ti is added in the range of 0.005 to 0.1%.
  • the component composition of the present disclosure is intended to further improve the strength and toughness of a steel sheet by selecting one or more selected from Cu, Ni, and Cr in the following range. Can be arbitrarily contained.
  • Cu 0.50% or less Cu is an element effective for improving toughness and increasing strength. To obtain this effect, it is preferable to contain 0.05% or more. Therefore, when Cu is added, the upper limit is 0.50%.
  • Ni 0.10% or less
  • Ni is an element effective for improving toughness and increasing strength. To obtain this effect, it is preferable to contain 0.01% or more, but more than 0.10% When Ni is added, the upper limit is 0.10% when Ni is added in order to easily generate a fine crack called a Fischer in an environment having a low hydrogen sulfide partial pressure of less than 1 bar. Preferably, it is 0.02% or less.
  • Cr 0.50% or less Cr, like Mn, is an element effective for obtaining sufficient strength even at low C, and it is preferable to contain 0.05% or more in order to obtain this effect. If the amount is too large, the hardenability becomes excessive, so that the dislocation density described later increases, and the SSCC resistance deteriorates. In addition, weldability also deteriorates. Therefore, when adding Cr, the upper limit is 0.50%.
  • the component composition of the present disclosure may further contain at least one selected from V, Zr, Mg, and REM in the following range.
  • V 0.005 to 0.1%
  • Zr 0.0005 to 0.02%
  • Mg 0.0005 to 0.02%
  • REM 0.0005 to 0.02%
  • V is an element that can be arbitrarily added to enhance the strength and toughness of the steel sheet. If the content is less than 0.005%, the effect of the addition is poor. On the other hand, if the content exceeds 0.1%, the toughness of the welded portion is degraded. preferable.
  • Zr, Mg and REM are elements that can be arbitrarily added in order to increase the toughness through refinement of the crystal grains and to increase the crack resistance through the control of the properties of inclusions. If the content of any of these elements is less than 0.0005%, the effect of the addition is poor, while if the content exceeds 0.02%, the effect is saturated. It is preferably in the range of 02%.
  • the present disclosure discloses a technique for improving the SSCC resistance of a high-strength steel pipe using a high-strength steel plate for a sour-resistant linepipe. It is necessary to satisfy at the same time. For example, it is preferable that the CP value obtained by the following equation (1) be 1.00 or less. Note that 0 may be substituted for an element that is not added.
  • the CP value is a formula devised for estimating the material of the central segregation portion from the content of each alloy element.
  • the higher the CP value of the above formula (1) the higher the component concentration of the central segregation portion. And the hardness of the center segregation part increases. Therefore, by setting the CP value obtained in the above equation (1) to 1.00 or less, it becomes possible to suppress the occurrence of cracks in the HIC test.
  • the lower the CP value the lower the hardness of the central segregation portion. Therefore, when higher HIC resistance is required, the upper limit may be set to 0.95.
  • N is an element inevitably contained in steel, but if its content is 0.007% or less, preferably 0.006% or less, it is acceptable in the present invention.
  • the steel structure of the high-strength steel plate for a sour-resistant line pipe of the present disclosure will be described.
  • the steel structure needs to be a bainite structure.
  • a hard phase such as martensite or island-like martensite (MA)
  • MA island-like martensite
  • the steel structure of the surface layer has a bainite structure.
  • Parts other than the surface layer also have a bainite structure, and the structure at the center of the plate thickness on behalf of the part may be a bainite structure.
  • the bainite structure includes a structure called bainitic ferrite or granular ferrite that transforms during accelerated cooling or after accelerated cooling that contributes to transformation strengthening.
  • different types of structures such as ferrite, martensite, pearlite, island martensite, and retained austenite are mixed in the bainite structure, the strength, toughness, and surface hardness increase. The lower the fraction, the better.
  • the volume fraction of the structure other than the bainite phase is sufficiently low, their influence is negligible, so that a certain amount is permissible.
  • the total volume of steel structures other than bainite (ferrite, martensite, pearlite, island-like martensite, retained austenite, etc.) is less than 5% by volume, there is no significant effect, and therefore, it is acceptable. Shall be performed.
  • the structure of the extremely surface layer portion of the steel sheet specifically, the steel structure of 0.25 mm below the surface of the steel sheet, has a dislocation density of 1. It is important to have a bainite structure of 0 ⁇ 10 14 to 7.0 ⁇ 10 14 (m ⁇ 2 ). Since the dislocation density decreases during the coating process after pipe forming, if the dislocation density at 0.25 mm below the steel sheet surface is 7.0 ⁇ 10 14 (m ⁇ 2 ) or less, the increase in hardness due to age hardening is minimized. Can be minimized.
  • dislocation density 0.25 mm below the surface of the steel sheet exceeds 7.0 ⁇ 10 14 (m ⁇ 2 )
  • the dislocation density does not decrease in the coating process after pipe forming, and the hardness increases significantly by age hardening. Degrades SSCC resistance.
  • a preferred range of dislocation density for obtaining good SSCC resistance after pipe forming is 6.0 ⁇ 10 14 (m ⁇ 2 ) or less.
  • the dislocation density at 0.25 mm below the steel sheet surface is less than 1.0 ⁇ 10 14 (m ⁇ 2 )
  • the steel sheet cannot maintain its strength.
  • the same superfluous layer part in the range of 0.25 mm in depth from the steel sheet surface has the same dislocation density. As a result, the effect of improving the SSCC resistance can be obtained.
  • the HV 0.1 at 0.25 mm below the surface is 230 or less. From the viewpoint of ensuring the SSCC resistance of the steel pipe, it is important to suppress the surface hardness of the steel sheet. However, by setting the HV 0.1 at 0.25 mm below the surface of the steel sheet to 230 or less, 250% or less after the pipe is formed. After a coating heat treatment process at 1 ° C. for 1 hour, HV0.1 at 0.25 mm below the surface can be suppressed to 260 or less, and SSCC resistance can be ensured.
  • the dispersion of Vickers hardness at 0.25 mm below the steel sheet surface is 30 HV or less at 3 ⁇ when the standard deviation is ⁇ . If 3 ⁇ when measuring Vickers hardness at 0.25 mm below the surface of the steel sheet is more than 30 HV, the hardness variation in the extreme surface layer of the steel sheet, that is, the presence of a locally high hardness part in the extreme surface layer, This is because degradation of the SSCC resistance starts from the starting point. When obtaining the standard deviation ⁇ , it is preferable to measure Vickers hardness at 100 points or more.
  • the dispersion of Vickers hardness in the thickness direction is 30 HV or less at 3 ⁇ when the standard deviation is ⁇ .
  • the high-strength steel plate of the present disclosure is a steel plate for a steel pipe having an API of 5L and a strength of X60 grade or more, it has a tensile strength of 520 MPa or more.
  • the rolling end temperature at the steel sheet surface temperature is set to the required base material toughness and rolling. It is necessary to set in consideration of efficiency. From the viewpoint of improving the strength and the HIC resistance, it is preferable that the rolling end temperature be equal to or higher than the Ar 3 transformation point at the steel sheet surface temperature.
  • the Ar 3 transformation point means a ferrite transformation start temperature during cooling, and can be determined by, for example, the following formula from steel components. Further, in order to obtain a high base material toughness, it is desirable that the rolling reduction in a temperature range of 950 ° C.
  • austenite non-recrystallization temperature range is 60% or more.
  • the surface temperature of the steel sheet can be measured with a radiation thermometer or the like.
  • Ar 3 (° C.) 910-310 [% C] -80 [% Mn] -20 [% Cu] -15 [% Cr] -55 [% Ni] -80 [% Mo]
  • [% X] indicates the content (% by mass) of X element in steel.
  • Cooling start temperature (Ar 3 ⁇ 10 ° C.) or more at the steel sheet surface temperature If the steel sheet surface temperature at the start of cooling is low, the amount of ferrite generated before controlled cooling increases, and in particular, the temperature drop from the Ar 3 transformation point is 10 If the temperature exceeds 0 ° C, ferrite exceeding 5% in volume fraction is generated, and the strength decreases and the HIC resistance deteriorates. Therefore, the surface temperature of the steel sheet at the start of cooling is (Ar 3 -10 ° C) or more. . The steel sheet surface temperature at the start of cooling is equal to or lower than the rolling end temperature.
  • Average cooling rate from 750 ° C to 550 ° C at a steel sheet temperature 0.25mm below the steel sheet surface 50 ° C / s or less Average cooling rate from 750 ° C to 550 ° C at a steel sheet temperature 0.25mm below the steel sheet surface is 50 ° C / If it exceeds s, the dislocation density at a depth of 0.25 mm below the surface of the steel sheet will exceed 7.0 ⁇ 10 14 (m ⁇ 2 ). As a result, the HV0.1 at 0.25 mm below the surface of the steel plate exceeds 230, and after the coating process after pipe making, the HV0.1 at 0.25 mm below the surface exceeds 260, deteriorating the SSCC resistance of the steel tube. I do.
  • the average cooling rate is set to 50 ° C./s or less. It is preferably at most 45 ° C / s, more preferably at most 40 ° C / s.
  • the lower limit of the average cooling rate is not particularly limited, but if the cooling rate is excessively low, ferrite or pearlite is generated, resulting in insufficient strength. From the viewpoint of preventing this, it is preferable to set the average cooling rate to 20 ° C./s or more.
  • Average cooling rate from 750 ° C to 550 ° C at an average temperature of steel sheet 15 ° C / s or more If the average cooling rate from 750 ° C to 550 ° C at an average temperature of steel sheet is less than 15 ° C / s, bainite structure is not obtained and strength is obtained. This results in a decrease and a decrease in HIC resistance. Therefore, the cooling rate at the average temperature of the steel sheet is set to 15 ° C./s or more. From the viewpoint of variations in the strength and hardness of the steel sheet, the average cooling rate of the steel sheet is preferably set to 20 ° C./s or more. The upper limit of the average cooling rate is not particularly limited, but is preferably 80 ° C./s or less so that the low-temperature transformation product is not excessively generated.
  • Average cooling rate from 550 ° C at the temperature of the steel sheet at 0.25 mm below the surface of the steel sheet to the temperature at which cooling is stopped 150 ° C / s or more
  • stable cooling at 550 ° C or less at the steel sheet temperature of 0.25 mm below the steel sheet surface stable nucleate boiling Cooling in a state is necessary, and an increase in the water density is indispensable.
  • the average cooling rate is set to 150 ° C./s or more. Preferably it is 170 ° C./s or more.
  • the upper limit of the average cooling rate is not particularly limited, but is preferably set to 250 ° C./s or less due to facility restrictions.
  • the 0.25 mm below the surface of the steel sheet and the average temperature of the steel sheet cannot be directly measured physically.
  • the surface temperature at the start of cooling measured by a radiation thermometer and the surface temperature at the target stop of cooling are also measured.
  • the temperature distribution in the thickness cross section can be obtained in real time by a difference calculation using a process computer.
  • the temperature at 0.25 mm below the steel sheet surface in the temperature distribution is referred to as “the steel sheet temperature at 0.25 mm below the steel sheet surface” in this specification, and the average value of the temperature in the thickness direction in the temperature distribution is referred to as “the steel sheet in this specification. Average temperature ".
  • Cooling stop temperature 250 to 550 ° C at the average temperature of the steel sheet
  • the bainite phase is formed by rapid cooling to 250 to 550 ° C., which is a temperature range of bainite transformation, by controlled cooling. If the cooling stop temperature exceeds 550 ° C., bainite transformation is incomplete and sufficient strength cannot be obtained. If the cooling stop temperature is less than 250 ° C., the hardness of the surface layer increases significantly, and the dislocation density at 0.25 mm below the steel sheet surface exceeds 7.0 ⁇ 10 14 (m ⁇ 2 ). Deteriorates. In addition, the hardness of the center segregation part increases, and the HIC resistance also deteriorates. Therefore, in order to suppress the deterioration of the material uniformity in the steel sheet, the cooling stop temperature of the controlled cooling is set to 250 to 550 ° C. as the average temperature of the steel sheet.
  • Reheating temperature Average temperature of the steel sheet, exceeding the cooling stop temperature, and 450 to 600 ° C
  • Reheating temperature Average temperature of the steel sheet, exceeding the cooling stop temperature, and 450 to 600 ° C
  • the steel sheet is subjected to on-line reheating after rapid cooling to 250 to 550 ° C., which is a temperature range of bainite transformation, by controlled cooling.
  • the reheating the steel sheet is heated to a temperature higher than the cooling stop temperature to temper and soften the bainite phase, so that SSCC resistance can be improved.
  • the reheating temperature is lower than 450 ° C, the surface layer softening effect is insufficient, and if the reheating temperature is higher than 600 ° C, the strength is reduced and the DWTT (Drop Weight Tear Test) characteristic is deteriorated.
  • the reheating temperature is 450 to 600 ° C.
  • to perform reheating immediately after stopping the controlled cooling means to perform reheating within 120 seconds after stopping the control cooling.
  • cooling after reheating is basically air cooling.
  • the high-strength steel sheet of the present disclosure is formed into a tubular shape by press bend forming, roll forming, UOE forming, and the like, and by welding the butted portions, the material uniformity in the steel sheet suitable for transporting crude oil and natural gas is excellent. It is possible to manufacture high-strength steel pipes (such as UOE steel pipes, ERW steel pipes, and spiral steel pipes) for sour resistant line pipes.
  • UOE steel pipes beveling the end of the steel plate, forming into a steel pipe shape by C-press, U-press, O-press, then seam-welding the butt portion by inner surface welding and outer surface welding, and further if necessary It is manufactured through an expansion process.
  • any welding method may be used as long as sufficient joint strength and joint toughness can be obtained.
  • Steel (steel types A to M) having the composition shown in Table 1 was formed into a slab by a continuous casting method, heated to the temperature shown in Table 2, and then subjected to hot rolling at the rolling end temperature and rolling reduction shown in Table 2. Thus, a steel plate having a plate thickness shown in Table 2 was obtained. Thereafter, the steel sheet was subjected to controlled cooling using a water-cooled controlled cooling device under the conditions shown in Table 2. Immediately thereafter, the steel sheet was reheated using an online induction heating apparatus so that the average temperature of the steel sheet became the “reheating temperature” in Table 2.
  • the Vickers hardness (HV0.1) was measured until the standard deviation ⁇ was obtained.
  • Table 2 shows the value of 3 ⁇ as hardness variation in the thickness direction.
  • the measurement at HV0.1 instead of the commonly used HV10 is because the indentation is reduced by measuring at HV0.1, so that the hardness information at a position closer to the surface and the sensitivity to the microstructure are more sensitive. This is because it is possible to provide information on the hardness of the object.
  • Dislocation density A sample for X-ray diffraction was collected from a position having an average hardness, the sample surface was polished to remove scale, and X-ray diffraction measurement was performed at a position 0.25 mm below the steel sheet surface. The method of converting the dislocation density from the strain obtained from the half width ⁇ of the X-ray diffraction measurement was used. In a diffraction intensity curve obtained by ordinary X-ray diffraction, two K ⁇ 1 rays and K ⁇ 2 rays having different wavelengths are overlapped with each other, and are separated by the Rachinger method. The Williamsson-Hall method described below is used for distortion extraction.
  • the spread of the half width is affected by the crystallite size D and the strain ⁇ , and can be calculated by the following equation as the sum of both factors.
  • strain ⁇ is calculated from the slope of the straight line.
  • the diffraction lines used for calculation are (110), (211), and (220).
  • ⁇ 14.4 ⁇ 2 / b 2 was used.
  • ⁇ means the peak angle calculated by the ⁇ -2 ⁇ method of X-ray diffraction
  • ⁇ means the wavelength of X-ray used in X-ray diffraction
  • b is the Burgers vector of Fe ( ⁇ ), which was 0.25 nm in this embodiment.
  • SSCC resistance was evaluated by forming a pipe using a part of each of these steel sheets.
  • the pipe is manufactured by beveling the end of the steel plate, forming it into a steel pipe shape by C press, U press, and O press, then seam welding the inner and outer butt joints by submerged arc welding and then expanding the pipe. did.
  • a coupon cut out from the obtained steel pipe was flattened, and a 5 ⁇ 15 ⁇ 115 mm SSCC test piece was collected from the inner surface of the steel pipe. At this time, the inner surface, which is the surface to be inspected, was left blackened in order to leave the state of the outermost layer.
  • the HIC resistance was examined by an HIC test of immersion for 96 hours at a partial pressure of hydrogen sulfide of 1 bar using a NACE standard TM0177 Solution A solution. In addition, using a NACE standard TM0177 Solution B solution, an HIC test was conducted by immersion for 96 hours at a partial pressure of hydrogen sulfide: 0.1 bar + a partial pressure of carbon dioxide: 0.9 bar. The HIC resistance was evaluated as good when the crack length ratio (CLR) was 15% or less in the HIC test, and evaluated as x when it exceeded 15%. Table 2 shows the results.
  • CLR crack length ratio
  • the target range of the present invention is a high-strength steel sheet for a sour-resistant line pipe having a tensile strength of 520 MPa or more, a microstructure of bainite at both the 0.25 mm position and the t / 2 position below the surface, and an HV of 0.1 at a position of 0.25 mm below the surface. Is 230 or less, no crack is observed in the SSCC test in a high-strength steel pipe formed using the steel plate, and the crack length ratio (CLR) is 15% or less in the HIC test.
  • CLR crack length ratio
  • No. 1 to No. 15 is an invention example in which the component composition and the production conditions satisfy the appropriate range of the present invention.
  • the tensile strength of the steel sheet is 520 MPa or more
  • the microstructure is 0.25 mm below the surface and the t / 2 position
  • the microstructure is bainite
  • the HV0.1 at 0.25 mm below the surface is 230 or less.
  • the SSCC resistance and HIC resistance of the formed high-strength steel pipe were also good.
  • No. 16-No. 23 is a comparative example in which the component composition is within the range of the present invention, but the production conditions are out of the range of the present invention.
  • No. Sample No. 16 had low strength because the slab heating temperature was low, so that microstructure homogenization and solid solution of carbide were insufficient.
  • No. Sample No. 17 had a low cooling start temperature and had a layered structure in which ferrite was precipitated, and thus had low strength and deteriorated HIC resistance after pipe formation.
  • the controlled cooling conditions were out of the range of the present invention, the bainite structure was not obtained in the center of the plate thickness as the microstructure, and the ferrite + pearlite structure was obtained. Has deteriorated. No.
  • a steel pipe such as an electric resistance welded steel pipe, a spiral steel pipe, or a UOE steel pipe
  • this steel sheet can be suitably used for transporting crude oil or natural gas containing hydrogen sulfide that requires sour resistance. .

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PCT/JP2019/037698 2018-09-28 2019-09-25 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管 WO2020067210A1 (ja)

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EP19864846.1A EP3859026B1 (en) 2018-09-28 2019-09-25 High strength steel plate for sour-resistant line pipe and method for manufacturing same, and high strength steel pipe using high strength steel plate for sour-resistant line pipe
BR112021005599-1A BR112021005599B1 (pt) 2018-09-28 2019-09-25 Chapa de aço de alta resistência para tubulação resistente à acidez e método para fabricação da mesma e tubo de aço de alta resistência que usa chapa de aço de alta resistência para tubulação resistente à acidez
JP2020524425A JP6825749B2 (ja) 2018-09-28 2019-09-25 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管
RU2021112075A RU2767261C1 (ru) 2018-09-28 2019-09-25 Высокопрочная стальная пластина для кислотостойкого трубопровода и способ получения стальной пластины, высокопрочная стальная труба, в которой используется высокопрочная стальная пластина для кислотостойкого трубопровода
KR1020217011928A KR102524176B1 (ko) 2018-09-28 2019-09-25 내사워 라인 파이프용 고강도 강판 및 그 제조 방법 그리고 내사워 라인 파이프용 고강도 강판을 사용한 고강도 강관
CN201980063051.XA CN112752858B (zh) 2018-09-28 2019-09-25 耐酸性管线管用高强度钢板和其制造方法以及使用耐酸性管线管用高强度钢板的高强度钢管

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2022239591A1 (ja) * 2021-05-14 2022-11-17 Ｊｆｅスチール株式会社 高強度熱延鋼板およびその製造方法、並びに高強度電縫鋼管およびその製造方法
WO2023162571A1 (ja) * 2022-02-24 2023-08-31 Ｊｆｅスチール株式会社 鋼板およびその製造方法

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2022244977A1 (ko) 2021-05-18 2022-11-24 주식회사 엘지에너지솔루션 리튬 이차전지용 양극 및 이를 포함하는 리튬 이차전지

Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0711896B2 (ja) 1988-05-25 1995-02-08 株式会社ケンウッド 光ディスク再生装置
JPH0796133B2 (ja) 1990-01-24 1995-10-18 三菱電機株式会社 板状材料の成形加工法
JPH0951428A (ja) 1995-08-09 1997-02-18 Fuji Photo Film Co Ltd 画像データの補間演算方法および装置
JPH0951429A (ja) 1995-08-09 1997-02-18 Fuji Photo Film Co Ltd 画像データ補間演算方法および装置
JP2002327212A (ja) 2001-02-28 2002-11-15 Nkk Corp 耐サワーラインパイプ用鋼板の製造方法
JP2010196163A (ja) * 2009-01-30 2010-09-09 Jfe Steel Corp 低温靭性に優れた厚肉高張力熱延鋼板およびその製造方法
JP2012077331A (ja) * 2010-09-30 2012-04-19 Jfe Steel Corp 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管
JP2013139630A (ja) * 2011-12-09 2013-07-18 Jfe Steel Corp 鋼板内の材質均一性に優れた耐サワーラインパイプ用高強度鋼板とその製造方法
WO2014041801A1 (ja) * 2012-09-13 2014-03-20 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
WO2018179512A1 (ja) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管
WO2018181564A1 (ja) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0957327A (ja) 1995-08-22 1997-03-04 Sumitomo Metal Ind Ltd 厚鋼板のスケール除去方法
JPH10237583A (ja) * 1997-02-27 1998-09-08 Sumitomo Metal Ind Ltd 高張力鋼およびその製造方法
JP3951429B2 (ja) 1998-03-30 2007-08-01 Ｊｆｅスチール株式会社 板厚方向材質差の小さい高張力鋼板の製造方法
JP3951428B2 (ja) 1998-03-30 2007-08-01 Ｊｆｅスチール株式会社 板厚方向材質差の小さい高張力鋼板の製造方法
JP3796133B2 (ja) 2000-04-18 2006-07-12 新日本製鐵株式会社 厚鋼板冷却方法およびその装置
JP3711896B2 (ja) 2001-06-26 2005-11-02 Ｊｆｅスチール株式会社 高強度ラインパイプ用鋼板の製造方法
JP4305216B2 (ja) * 2004-02-24 2009-07-29 Ｊｆｅスチール株式会社 溶接部の靭性に優れる耐サワー高強度電縫鋼管用熱延鋼板およびその製造方法
JP5110989B2 (ja) * 2007-07-12 2012-12-26 株式会社神戸製鋼所 脆性亀裂伝播停止特性に優れた大入熱溶接用厚鋼板
CA2844718C (en) * 2009-01-30 2017-06-27 Jfe Steel Corporation Thick high-tensile-strength hot-rolled steel sheet having excellent low-temperature toughness and manufacturing method thereof
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
JP5516784B2 (ja) * 2012-03-29 2014-06-11 Ｊｆｅスチール株式会社 低降伏比高強度鋼板およびその製造方法並びにそれを用いた高強度溶接鋼管
JP5516785B2 (ja) * 2012-03-29 2014-06-11 Ｊｆｅスチール株式会社 低降伏比高強度鋼板およびその製造方法並びにそれを用いた高強度溶接鋼管
JP6165088B2 (ja) * 2013-03-29 2017-07-19 株式会社神戸製鋼所 耐水素誘起割れ性と溶接熱影響部の靭性に優れた鋼板およびラインパイプ用鋼管
CN107406948B (zh) * 2015-03-26 2019-03-08 杰富意钢铁株式会社 结构管用厚壁钢板、结构管用厚壁钢板的制造方法和结构管

Patent Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0711896B2 (ja) 1988-05-25 1995-02-08 株式会社ケンウッド 光ディスク再生装置
JPH0796133B2 (ja) 1990-01-24 1995-10-18 三菱電機株式会社 板状材料の成形加工法
JPH0951428A (ja) 1995-08-09 1997-02-18 Fuji Photo Film Co Ltd 画像データの補間演算方法および装置
JPH0951429A (ja) 1995-08-09 1997-02-18 Fuji Photo Film Co Ltd 画像データ補間演算方法および装置
JP2002327212A (ja) 2001-02-28 2002-11-15 Nkk Corp 耐サワーラインパイプ用鋼板の製造方法
JP2010196163A (ja) * 2009-01-30 2010-09-09 Jfe Steel Corp 低温靭性に優れた厚肉高張力熱延鋼板およびその製造方法
JP2012077331A (ja) * 2010-09-30 2012-04-19 Jfe Steel Corp 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管
JP2013139630A (ja) * 2011-12-09 2013-07-18 Jfe Steel Corp 鋼板内の材質均一性に優れた耐サワーラインパイプ用高強度鋼板とその製造方法
WO2014041801A1 (ja) * 2012-09-13 2014-03-20 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
WO2018179512A1 (ja) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管
WO2018181564A1 (ja) * 2017-03-30 2018-10-04 Ｊｆｅスチール株式会社 耐サワーラインパイプ用高強度鋼板およびその製造方法並びに耐サワーラインパイプ用高強度鋼板を用いた高強度鋼管

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2022239591A1 (ja) * 2021-05-14 2022-11-17 Ｊｆｅスチール株式会社 高強度熱延鋼板およびその製造方法、並びに高強度電縫鋼管およびその製造方法
JP7211566B1 (ja) * 2021-05-14 2023-01-24 Ｊｆｅスチール株式会社 高強度熱延鋼板およびその製造方法、並びに高強度電縫鋼管およびその製造方法
EP4321632A4 (en) * 2021-05-14 2025-01-01 JFE Steel Corporation High-strength hot-rolled steel sheet and manufacturing method therefor, and high-strength electric resistance welded steel pipe and manufacturing method therefor
WO2023162571A1 (ja) * 2022-02-24 2023-08-31 Ｊｆｅスチール株式会社 鋼板およびその製造方法
TWI826257B (zh) * 2022-02-24 2023-12-11 日商Ｊｆｅ鋼鐵股份有限公司 鋼板及其製造方法
JP7601218B2 (ja) 2022-02-24 2024-12-17 Ｊｆｅスチール株式会社 鋼板およびその製造方法

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BR112021005599A2 (pt) 2021-06-29
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