WO2021020220A1 - 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 PDFInfo
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Definitions
- the present invention relates to a high-strength steel plate for sour-resistant line pipes having excellent material uniformity in the steel plate, which is suitable for use in line pipes used for transporting crude oil and natural gas, and a method for manufacturing the same.
- the present invention also relates to a high-strength steel pipe using the above-mentioned high-strength steel plate for sour-resistant pipes.
- a line pipe is manufactured by molding a steel plate manufactured by a thick plate mill or a hot-rolling mill into a steel pipe by UOE molding, press bend molding, roll molding, or the like.
- the line pipe used for transporting crude oil containing hydrogen sulfide and natural gas has hydrogen sulfide-induced cracking resistance (HIC (Hydrogen Induced Cracking) resistance) and sulfide resistance, in addition to strength, toughness, and weldability.
- So-called sour resistance such as stress corrosion cracking resistance (SSCC (Sulfide Stress Corrosion Cracking) resistance) is required.
- SSCC Stress Corrosion Cracking resistance
- HIC hydrogen ions due to the corrosion reaction are adsorbed on the surface of the steel material, penetrate into the steel as atomic hydrogen, and diffuse and accumulate around non-metal inclusions such as MnS in the steel and the hard phase 2 structure.
- TMCP Thermo-Mechanical Control Process
- TMCP Thermo-Mechanical Control Process
- the surface layer portion of the steel sheet is rapidly cooled, so that the hardness of the surface layer portion is higher than that inside the steel sheet.
- the steel sheet is formed into a tubular shape, it is work-hardened, so that the hardness of the surface layer portion increases and the SSCC resistance decreases.
- Patent Document 1 the cooling step after hot rolling is multi-stage cooling, so that the maximum hardness in the range from the surface of the steel pipe to a depth of 1.0 mm is 250 Hv.
- Patent Document 2 proposes to reduce the hardness of a steel pipe to 220 Hv or less by low-temperature heat treatment to improve HIC resistance.
- Patent Document 1 it is possible to improve the SSCC resistance in an environment containing hydrogen sulfide having a partial pressure exceeding 0.1 MPa (1 bar), but in an environment where the partial pressure of hydrogen sulfide is low, a fine particle called Fisher.
- the SSCC caused by the crack is not considered.
- Patent Document 2 improves SSCC resistance in an environment with a high partial pressure of hydrogen sulfide, as HIC resistance is evaluated in a NACE test performed by saturating hydrogen sulfide gas in a solution. It does not give a means.
- the present invention is excellent not only in HIC resistance but also in SSCC resistance in an environment containing hydrogen sulfide having a partial pressure of more than 1 bar and SSCC resistance in an environment having a low hydrogen sulfide partial pressure.
- An object of the present invention is to provide a high-strength steel plate for a sour line pipe together with an advantageous manufacturing method thereof.
- Another object of the present invention is to propose a high-strength steel pipe using the above-mentioned high-strength steel plate for sour-resistant pipes.
- the present inventors have repeated many experiments and studies on the composition, microstructure and manufacturing conditions of steel materials in order to ensure SSCC resistance in a harsher corrosive environment.
- the steel structure of 0.25 mm below the surface of the steel sheet is made into a bainite structure, and the KAM (Kernel Average Missionation) value in the bainite is 0.4 or more.
- the KAM (Kernel Average Missionation) value in the bainite is 0.4 or more. It was found that by setting the area ratio of a certain crystal grain to 50% or less, the maximum hardness of 0.25 mm below the surface of the steel sheet can be set to 230 or less at HV0.1, and the SSCC resistance of the steel pipe is improved.
- the present invention has been made based on these findings.
- the gist structure of the present invention is as follows. [1] In terms of mass%, C: 0.020 to 0.080%, Si: 0.01 to 0.50%, Mn: 0.50 to 1.80%, P: 0.015% or less, S: 0.0015% or less, Al: 0.010 to 0.080%, N: 0.0010 to 0.0080%, Mo: 0.01 to 0.50% and Ca: 0.0005 to 0.0050%. It has a component composition that is contained and the balance is Fe and unavoidable impurities.
- the steel structure at 0.25 mm below the surface of the steel sheet is defined as the bainite structure, and the area ratio of the crystal grains having a KAM (Kernel Average Misorientation) value of 0.4 or more in the bainite is 50% or less.
- the maximum value of Vickers hardness at 0.25 mm below the surface of the steel sheet is 230 Hv or less.
- the KAM value is the average value of the orientation difference between each pixel (0.3 ⁇ m pitch) in the crystal grain and the adjacent pixel calculated from the EBSD (Electron Backscatter Diffraction) analysis.
- the above-mentioned component composition further contains at least one selected from Cu: 0.30% or less, Ni: 0.10% or less, and Cr: 0.50% or less in mass%.
- the component composition is, in mass%, Nb: 0.005 to 0.1%, V: 0.005 to 0.1%, Ti: 0.005 to 0.1%, Zr: 0. [1] or [2] above, which contains at least one selected from 0005 to 0.02%, Mg: 0.0005 to 0.02%, and REM: 0.0005 to 0.02%.
- a steel piece having the component composition according to the above [1], [2] or [3] is heated to a temperature of 1000 to 1300 ° C. and then hot-rolled to obtain a steel sheet. After that, with respect to the steel sheet Cooling at the start of the steel sheet surface temperature: (Ar 3 -10 °C) or higher, Average cooling rate from 750 ° C to 550 ° C at steel plate temperature 0.25 mm below the surface of the steel plate: 20 to 50 ° C / s, Average cooling rate from 750 ° C to 550 ° C at average steel plate temperature: 15 ° C / s or higher and cooling stop temperature at steel plate temperature 0.25 mm below the surface of the steel sheet: 250 to 550 ° C.
- the high-strength steel pipe for sour-resistant pipes of the present invention and the high-strength steel pipe using the high-strength steel plate for sour-resistant pipes have not only HIC resistance but also resistance in an environment containing hydrogen sulfide having a partial pressure exceeding 1 bar. It has excellent SSCC resistance and SSCC resistance in an environment with a low hydrogen sulfide partial pressure of 1 bar or less. Further, according to the method for producing a high-strength steel plate for sour line pipes of the present invention, not only HIC resistance but also SSCC resistance in an environment containing more than 1 bar of hydrogen sulfide and low hydrogen sulfide partial pressure of 1 bar or less are low. It is possible to manufacture a high-strength steel plate for sour line pipes, which has excellent SSCC resistance in the environment.
- C 0.020 to 0.080% C effectively contributes to the improvement of strength, but if the content is less than 0.020%, sufficient strength cannot be secured. Therefore, the amount of C is set to 0.020% or more, preferably 0.025% or more. On the other hand, if the amount of C exceeds 0.080%, the hardness of the surface layer portion and the central segregation portion increases during accelerated cooling, so that SSCC resistance and HIC resistance deteriorate. In addition, toughness also deteriorates. Therefore, the amount of C is set to 0.080% or less, preferably 0.070% or less.
- Si 0.01-0.50% Si is added for deoxidation, but if the content is less than 0.01%, the deoxidizing effect is not sufficient, so the amount of Si is 0.01% or more, preferably 0.05% or more. On the other hand, if the Si amount exceeds 0.50%, the toughness and weldability deteriorate. Therefore, the Si amount is 0.50% or less, preferably 0.45% or less.
- Mn 0.50 to 1.80% Mn effectively contributes to the improvement of strength and toughness, but the effect is not sufficiently exhibited when the content is less than 0.50%. Therefore, the amount of Mn is 0.50% or more, preferably 0.80% or more. On the other hand, if the amount of Mn exceeds 1.80%, the hardness of the surface layer portion and the central segregation portion increases during accelerated cooling, so that SSCC resistance and HIC resistance deteriorate. Weldability also deteriorates. Therefore, the amount of Mn is 1.80%, preferably 1.70% or less.
- P 0.015% or less
- P is an unavoidable impurity element, which deteriorates weldability and increases the hardness of the surface layer portion and the central segregation portion, thereby deteriorating SSCC resistance and HIC resistance. If it exceeds 0.015%, the tendency becomes remarkable, so the upper limit is set to 0.015%. It is preferably 0.008% or less. The lower the content, the better, but from the viewpoint of refining cost, it is preferably 0.001% or more.
- S 0.0015% or less
- S is an unavoidable impurity element and is preferably a small amount because it becomes an MnS inclusion in steel and deteriorates HIC resistance, but up to 0.0015% is allowed and 0.0010%.
- the following is preferable.
- Al 0.010 to 0.080% Al is added as an antacid, but its effect is not sufficiently exhibited if it is less than 0.010%. Therefore, the amount of Al is 0.010% or more, preferably 0.015% or more. On the other hand, if the Al amount exceeds 0.080%, the cleanliness of the steel is lowered and the toughness is deteriorated. Therefore, the Al amount is set to 0.080% or less, preferably 0.070% or less.
- N 0.0010 to 0.0080% N effectively contributes to the improvement of strength, but if the content is less than 0.0010%, sufficient strength cannot be secured. Therefore, the amount of N is 0.0010% or more, preferably 0.0015% or more. On the other hand, if it exceeds 0.0080%, the hardness of the surface layer portion and the central segregation portion increases during accelerated cooling, so that the SSCC resistance and the HIC resistance deteriorate. In addition, toughness also deteriorates. Therefore, the amount of N is 0.0080% or less, preferably 0.0070% or less.
- Mo 0.01-0.50% Mo is an element effective for improving toughness and increasing strength, and is an element effective for improving SSCC resistance regardless of the partial pressure of hydrogen sulfide.
- the present inventors have found that when a steel sheet containing Mo is subjected to an SSCC test, the surface of the steel sheet after the test is smoother than the surface of the steel sheet containing no Mo after the SSCC test. The mechanism is not always clear, but it is considered that this is related to the improvement of SSCC resistance. In order to obtain this effect, it is necessary to contain 0.01% or more, and preferably 0.10% or more.
- the amount of Mo is 0.50% or less, preferably 0.40% or less.
- Ca 0.0005-0.0050%
- Ca is an element effective for improving HIC resistance by controlling the morphology of sulfide-based inclusions, but its addition effect is not sufficient if it is less than 0.0005%. Therefore, the amount of Ca is 0.0005% or more, preferably 0.0008% or more. On the other hand, if it exceeds 0.0050%, not only the above-mentioned effect is saturated, but also the HIC resistance is deteriorated due to the decrease in the cleanliness of the steel. Therefore, the Ca amount is preferably 0.0050%. It shall be 0.0045% or less.
- component composition of the present disclosure includes one or more selected from Cu, Ni and Cr in the following range in order to further improve the strength and toughness of the steel sheet. Can be arbitrarily contained in.
- Cu 0.30% or less
- Cu is an element effective for improving toughness and increasing strength, and it is preferable to contain 0.05% or more in order to obtain this effect.
- the upper limit is 0.30%.
- it is 0.25% or less.
- Ni 0.10% or less
- Ni is an element effective for improving toughness and increasing strength, and it is preferable to contain 0.01% or more in order to obtain this effect.
- the upper limit is 0.10%.
- it is 0.02% or less.
- Cr 0.50% or less Cr is an element effective for obtaining sufficient strength even at low C like Mn, and it is preferable to contain 0.05% or more in order to obtain this effect.
- the upper limit is 0.50%. Preferably, it is 0.45% or less.
- the component composition of the present disclosure may further optionally contain one or more selected from Nb, V, Ti, Zr, Mg and REM within the following range.
- Nb 0.005 to 0.1%
- V 0.005 to 0.1%
- Ti 0.005 to 0.1%
- Zr 0.0005 to 0.02%
- Mg 0.0005 to One or more selected from 0.02% and REM: 0.0005 to 0.02%
- Nb, V and Ti are all elements that can be arbitrarily added in order to increase the strength and toughness of the steel sheet. If the content of each element is less than 0.005%, the effect is not sufficiently exhibited. Therefore, when these elements are added, it is preferably 0.005% or more. On the other hand, if the content of these elements exceeds 0.1%, the toughness of the welded portion deteriorates. Therefore, when they are added, it is preferably 0.1% or less.
- Zr, Mg and REM are elements that can be arbitrarily added in order to increase toughness through grain refinement and to increase crack resistance through control of inclusion properties. If the content of each element is less than 0.0005%, the effect is not sufficiently exhibited. Therefore, when these elements are added, it is preferably 0.0005% or more. On the other hand, if it exceeds 0.02%, the effect is saturated. Therefore, when it is added, it is preferably 0.02% or less.
- 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 line pipe, but it goes without saying that the sour resistance is also HIC resistance. It is necessary to be satisfied, and for example, the CP value obtained by the following equation (1) is preferably 1.00 or less. In addition, 0 may be substituted for the element which is not added.
- the CP value is an equation devised to estimate the material of the central segregation portion from the content of each alloy element, and the higher the CP value of the above equation (1), the higher the component concentration of the central segregation portion. Increases, and the hardness of the central segregated portion increases. Therefore, by setting the CP value obtained in the above equation (1) to 1.00 or less, it is possible to suppress the occurrence of cracks in the HIC test. Further, the lower the CP value, the lower the hardness of the central segregated portion. Therefore, when higher HIC resistance is required, the upper limit thereof may be 0.95.
- the balance other than the above elements consists of Fe and unavoidable impurities.
- the inclusion of other trace elements is not hindered as long as the effects of the present invention are not impaired.
- O is an element unavoidably contained in steel, but if its content is 0.0050% or less, preferably 0.0040% or less, it is acceptable in the present invention.
- the steel structure of the surface layer shall 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, which contributes to strengthening the transformation.
- bainitic ferrite or granular ferrite that transforms during accelerated cooling or after accelerated cooling, which contributes to strengthening the transformation.
- heterogeneous structures such as ferrite, martensite, pearlite, island-like martensite, and retained austenite are mixed in the bainite structure, the strength decreases, the toughness deteriorates, and the surface hardness increases. Therefore, structures other than the bainite phase The smaller the fraction, the better. However, if the volume fraction of the tissue other than the bainite phase is sufficiently low, those effects can be ignored, and a certain amount is acceptable.
- the total volume fraction of steel structures other than bainite is 5% or less, there is no significant effect and is acceptable. It shall be done.
- the bainite structure also has various forms depending on the cooling rate, but in the present disclosure, the structure of the polar surface layer of the steel sheet, specifically, the steel structure at 0.25 mm below the surface of the steel sheet is the bainite structure.
- the area ratio of the crystal grains having a KAM value of 0.4 or more is 50% or less.
- the KAM value reflects the local change in crystal orientation due to dislocations in the structure, and the higher the KAM value, the higher the degree of local deformation in the grain. Therefore, when the KAM value is high, it means that a large amount of transformation strain is introduced into the bainite structure, that is, it is a low temperature transformation phase.
- the low temperature transformation phase has a hard structure, if the proportion of the low temperature transformation phase is large, the SSCC resistance deteriorates.
- crystal grains having a KAM value of 0.4 or more are in a low temperature transformation phase, and therefore have high hardness, and when the ratio exceeds 50%, cracks are likely to propagate, so that SSCC resistance is improved. It deteriorates significantly. Therefore, among the above-mentioned bainite, it is necessary to set the area ratio of the crystal grains having a KAM value of 0.4 or more to 50% or less.
- the polar surface layer portion in the range from the surface of the steel sheet to the depth of 0.25 mm also has the same steel structure. As a result, the effect of improving SSCC resistance can be obtained.
- the steel structure at 0.25 mm below the inner surface of the steel sheet is defined as the bainite structure, the area ratio of the crystal grains having a KAM value of 0.4 or more is 50% or less, and the bainite is 0.25 mm below the surface.
- the high-strength steel sheet of the present disclosure is a steel sheet for steel pipes having a strength of X60 grade or higher of API 5L, it is assumed to have a tensile strength of 520 MPa or higher.
- slab heating temperature 1000-1300 ° C If the slab heating temperature is less than 1000 ° C., the solid solution of the carbide becomes insufficient and the amount of solid solution strengthening becomes small, so that the required strength cannot be obtained. On the other hand, if the temperature exceeds 1300 ° C., the crystal grains become extremely coarse and the toughness deteriorates. Therefore, the slab heating temperature is set to 1000 to 1300 ° C. It is preferably 1030 to 1250 ° C. It is assumed that the slab is heated to this temperature up to the center.
- the rolling end temperature at the steel sheet surface temperature is the required base material toughness and rolling. It is necessary to set in consideration of efficiency. From the viewpoint of improving the strength and HIC resistance, it is preferable that the rolling end temperature is equal to or higher than the Ar 3 transformation point at the steel sheet surface temperature.
- the Ar 3 transformation point means the ferrite transformation start temperature during cooling, and can be obtained from the components of steel, for example, by the following equation.
- 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 (mass%) of the X element in the steel.
- Cooling start temperature the steel plate surface temperature (Ar 3 -10 °C) or cooling at the start of the steel sheet surface temperature is low, becomes large ferrite amount before controlled cooling.
- Average cooling rate from 750 ° C to 550 ° C at 0.25 mm below the surface of the steel sheet 20 to 50 ° C / s It is important to slow down the average cooling rate from 750 ° C to 550 ° C as much as possible at the steel plate temperature 0.25 mm below the surface of the steel sheet to create a high-temperature transformation phase, and as the cooling rate slows down, the maximum hardness decreases. be able to. Since the temperature range from 750 ° C. to 550 ° C. is an important temperature range in bainite transformation, it is important to control the cooling rate in this temperature range.
- the average cooling rate is set to 50 ° C./s or less. It is preferably 30 ° C./s or less.
- the lower limit of the average cooling rate is not particularly limited, but if the cooling rate becomes excessively small, ferrite and pearlite are generated and the strength becomes insufficient. Therefore, from the viewpoint of preventing this, it is preferably 20 ° C./s or more. For cooling at a steel plate temperature of 550 ° C.
- the average cooling rate from 550 ° C. to the cooling stop temperature at the steel sheet temperature 0.25 mm below the surface of the steel sheet is preferably 150 ° C./s or more.
- the cooling rate at the average temperature of the steel sheet is set to 15 ° C./s or more.
- the cooling rate of the average steel sheet temperature is preferably 20 ° C./s or more.
- the upper limit of the average cooling rate is not particularly limited, but the average cooling rate is preferably 40 ° C./s or less so that the low temperature transformation phase is not excessively generated.
- the temperature at 0.25 mm below the surface of the steel plate and the average temperature of the steel plate cannot be physically measured directly, but the surface temperature at the start of cooling and the surface at the target cooling stop measured by a radiation thermometer. Based on the temperature, for example, the temperature distribution in the plate thickness cross section can be calculated by the difference calculation using a process computer, and the result can be obtained in real time.
- the temperature at 0.25 mm below the surface of the steel sheet in the temperature distribution is defined as "the temperature of the steel sheet at 0.25 mm below the surface of the steel sheet" in the present specification, and the average value of the temperatures in the thickness direction in the temperature distribution is the "steel plate” in the present specification. "Average temperature".
- Cooling stop temperature 250 to 550 ° C at the steel sheet temperature 0.25 mm below the steel sheet surface If the cooling stop temperature exceeds 550 ° C., the bainite transformation becomes incomplete and sufficient strength cannot be obtained. Further, when the cooling stop temperature is less than 250 ° C., the dislocation density becomes high, so that the hardness of the surface layer portion increases remarkably when the pipe is formed, and the SSCC resistance deteriorates.
- High-strength steel pipe The high-strength steel sheet of the present disclosure is formed into a tubular shape by press bend forming, roll forming, UOE forming, etc., and then the butt portion is welded to provide excellent material uniformity in the steel sheet suitable for transporting crude oil and natural gas.
- High-strength steel pipes for sour-resistant pipes UOE steel pipes, welded steel pipes, spiral steel pipes, etc.
- UOE steel pipes, welded steel pipes, spiral steel pipes, etc. can be manufactured.
- the high-strength steel plate of the present disclosure for the steel pipe it is possible to manufacture a steel pipe having excellent SSCC resistance even in the presence of a high hardness region of the welded portion.
- the end portion of a steel sheet is grooved, formed into a steel pipe shape by C press, U press, and O press, and then the butt portion is seam welded by inner surface welding and outer surface welding, and further, if necessary.
- the welding method may be any method as long as sufficient joint strength and joint toughness can be obtained, but from the viewpoint of excellent welding quality and manufacturing efficiency, submerged arc welding is preferably used. Further, it is possible to expand the steel pipe by seam welding the butt portion after forming the tubular shape by press bend forming.
- Steels (steel grades A to W) having the composition shown in Table 1 are made into slabs by a continuous casting method, heated to the temperatures shown in Table 2, and then hot-rolled at the rolling end temperature and rolling reduction ratio shown in Table 2.
- the steel plate with the thickness shown in Table 2 was used.
- the steel sheet was controlled-cooled using a water-cooled control cooling device under the conditions shown in Table 2. After that, the end of the steel sheet was grooved, formed into a steel pipe shape by C press, U press, and O press, and then the butt portion of the inner and outer surfaces was seam welded by submerged arc welding to make a steel pipe through a pipe expansion process. ..
- EBSD Electro Backscatter Diffraction
- Measurement step: 0.3 ⁇ m a Boundary map was created in which a portion having an orientation difference of 5 degrees or more was determined to be a grain boundary and drawn.
- a KAM map was created to depict the KAM value, which is the average value of the orientation differences between each pixel in the crystal grain and the adjacent pixel.
- the obtained Boundary map and KAM map were superposed, 100 crystal grains were randomly selected, and the bainite area ratio having a KAM value of 0.4 or more was measured. The results of these measurements are shown in Table 2.
- the SSCC resistance was obtained by flattening a test piece (coupon) cut out from the obtained steel pipe, and then collecting a 5 ⁇ 15 ⁇ 115 mm SSCC test piece from the inner surface of the steel pipe. At this time, in addition to the test piece containing only the base material not including the welded portion, a test piece containing both the welded portion and the base material was collected. The inner surface, which is the surface to be inspected, was left with black skin in order to retain the state of the outermost layer. That is, 0.25 mm below the surface of the steel sheet is included in the test piece.
- the SSCC test piece thus collected is loaded with a stress of 90% of the actual yield strength (0.5% YS) of each steel pipe, and using NACE standard TM0177 Solution A solution, hydrogen sulfide partial pressure: 1 bar, EFC16. The test was performed in accordance with the standard 4-point bending SSCC test. Similarly, using a NACE standard TM0177 Solution B solution, hydrogen sulfide partial pressure: 0.1 bar + carbon dioxide partial pressure: 0.9 bar was performed in accordance with the EFC16 standard 4-point bending SSCC test.
- the HIC resistance was examined by a 96-hour immersion HIC test at a partial pressure of hydrogen sulfide of 1 bar using a NACE standard TM0177 Solution A solution.
- hydrogen sulfide partial pressure 0.1 bar + carbon dioxide partial pressure: 0.9 bar was examined by a 96-hour immersion HIC test.
- the HIC resistance is judged to be excellent when the crack length ratio (CLR) is 10% or less in the HIC test, and is judged to be good when it is 15% or less, and exceeds 15%. The case was marked with x.
- CLR crack length ratio
- the target range of the present invention is a high-strength steel sheet for sour line pipes with a tensile strength of 520 MPa or more, a microstructure at 0.25 mm and t / 2 positions below the surface of the steel sheet, and a bainite structure and 0.25 mm below the surface of the steel sheet. It was determined that the maximum hardness of HV0.5 was 230 or less, no cracks were observed in the SSCC test, and the crack length ratio (CLR) was 15% or less in the HIC test.
- No. 1 to No. 9, No. 29 and 30 are examples of inventions in which the component composition and 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 a bainite structure at both the 0.25 mm position and the t / 2 position below the surface of the steel sheet
- the maximum hardness of HV0.5 at 0.25 mm below the surface is 230 or less.
- SSCC resistance and HIC resistance were also good.
- No. 10 to No. 18 the composition of the steel sheet is outside the scope of the present invention.
- No. 10 to No. 13 were inferior in SSCC resistance and HIC resistance because HV 0.5 exceeded 230.
- No. 14 since the amount of Cu in the steel sheet was excessive, the SSCC resistance in an environment where the partial pressure of hydrogen sulfide was low deteriorated.
- No. 15 since the amount of Ni in the steel sheet was excessive, the SSCC resistance in an environment where the partial pressure of hydrogen sulfide was low deteriorated.
- No. 16 and No. 17 were inferior in SSCC resistance and HIC resistance because HV 0.5 exceeded 230.
- No. 19-No. 23 is a comparative example in which the component composition is within the range of the present invention, but the production conditions are outside the range of the present invention.
- No. 19 since the slab heating temperature was low, the homogenization of the microstructure and the solid solution of carbides were insufficient, and the strength was low.
- No. No. 20 had a low cooling start temperature and had a layered structure in which ferrite was precipitated, so that the strength was low and the HIC resistance was deteriorated. In No.
- the controlled cooling conditions were outside the range of the present invention, and the microstructure was a ferrite + bainite structure, so that the strength was low and the HIC resistance was deteriorated.
- the average cooling rate from 750 to 550 ° C. at 0.25 mm below the surface of the steel sheet exceeded 50 ° C./s, and the KAM value at 0.25 mm below the surface exceeded 0.4. Therefore, HV0. 5 exceeded 230, and the SSCC resistance was inferior.
- the cooling stop temperature was low, the dislocation density at 0.25 mm below the surface was high, and the HV 0.5 exceeded 230, so that the SSCC resistance was inferior. No. In No. In No.
- the cooling stop temperature was high, the bainite transformation was incomplete, and sufficient strength could not be obtained.
- the average cooling rate from 750 to 550 ° C. at 0.25 mm below the surface of the steel sheet exceeds 50 ° C./s, and the cooling stop temperature is low, so that the KAM value at 0.25 mm below the surface is 0.4 or more. Since the area ratio exceeded 50%, the HV 0.5 exceeded 230 and the SSCC resistance was inferior.
- the composition of the steel sheet was out of the range of the present invention, and the strength was low.
- sour line pipes having excellent not only HIC resistance but also SSCC resistance in an environment containing more than 1 bar of hydrogen sulfide and SSCC resistance in an environment having a low partial pressure of hydrogen sulfide of less than 1 bar.
- High strength steel pipe can be supplied.
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Abstract
Description
[1]質量%で、C:0.020~0.080%、Si:0.01~0.50%、Mn:0.50~1.80%、P:0.015%以下、S:0.0015%以下、Al:0.010~0.080%、N:0.0010~0.0080%、Mo:0.01~0.50%およびCa:0.0005~0.0050%を含有し、残部がFeおよび不可避的不純物である成分組成を有し、
鋼板表面下0.25mmにおける鋼組織をベイナイト組織とし、当該ベイナイトにおける、KAM(Kernel Average Misorientation)値が0.4以上である結晶粒の面積率が50%以下であり、
鋼板表面下0.25mmにおけるビッカース硬さの最高値が230Hv以下であり、
引張強さが520MPa以上である耐サワーラインパイプ用高強度鋼板。
その後前記鋼板に対して、
冷却開始時の鋼板表面温度:(Ar3-10℃)以上、
鋼板表面下0.25mmにおける鋼板温度で750℃から550℃までの平均冷却速度:20~50℃/s、
鋼板平均温度で750℃から550℃までの平均冷却速度:15℃/s以上
および
鋼板表面下0.25mmにおける鋼板温度で冷却停止温度:250~550℃
の条件で冷却を行う耐サワーラインパイプ用高強度鋼板の製造方法。
まず、本開示による高強度鋼板の成分組成とその限定理由について説明する。以下の説明において%で示す単位は、特に断らない限り全て質量%である。
Cは、強度の向上に有効に寄与するが、含有量が0.020%未満では十分な強度が確保できないので、C量は0.020%以上とし、好ましくは0.025%以上とする。一方、C量が0.080%を超えると、加速冷却時に表層部や中心偏析部の硬さが上昇するため、耐SSCC性および耐HIC性が劣化する。また、靭性も劣化する。このため、C量は0.080%以下とし、好ましくは、0.070%以下とする。
Siは、脱酸のため添加するが、含有量が0.01%未満では脱酸効果が十分でないので、Si量は0.01%以上とし、好ましくは0.05%以上とする。一方、Si量が0.50%を超えると靭性や溶接性を劣化させるため、Si量は0.50%以下とし、好ましくは、0.45%以下とする。
Mnは、強度、靭性の向上に有効に寄与するが、含有量が0.50%未満ではその効果が十分には発現しない。このためMn量は0.50%以上とし、好ましくは0.80%以上とする。一方、Mn量が1.80%を超えると加速冷却時に表層部や中心偏析部の硬さが上昇するため、耐SSCC性および耐HIC性が劣化する。また、溶接性も劣化する。このため、Mn量は1.80%とし、好ましくは、1.70%以下とする。
Pは、不可避不純物元素であり、溶接性を劣化させるとともに、表層部や中心偏析部の硬さを上昇させることで、耐SSCC性および耐HIC性を劣化させる。0.015%を超えるとその傾向が顕著となるため、上限を0.015%とする。好ましくは0.008%以下とする。なお、含有量は低いほどよいが、精錬コストの観点からは、0.001%以上とすることが好ましい。
Sは、不可避不純物元素であり、鋼中においてはMnS介在物となり耐HIC性を劣化させるため少ないことが好ましいが、0.0015%までは許容され、0.0010%以下であることが好ましい。なお、含有量は低いほどよいが、精錬コストの観点から0.0002%以上とすることが好ましい。
Alは、脱酸剤として添加するが、0.010%未満ではその効果が十分には発現しない。このためAl量は0.010%以上とし、好ましくは0.015%以上とする。一方、Al量が0.080%を超えると鋼の清浄度が低下し、靱性が劣化するため、Al量は0.080%以下とし、好ましくは、0.070%以下とする。
Nは、強度の向上に有効に寄与するが、含有量が0.0010%未満では十分な強度が確保できない。このためN量は0.0010%以上とし、好ましくは0.0015%以上とする。一方、0.0080%を超えると、加速冷却時に表層部や中心偏析部の硬さが上昇するため、耐SSCC性および耐HIC性が劣化する。また、靭性も劣化する。このため、N量は0.0080%以下とし、好ましくは、0.0070%以下とする。
Moは、靭性の改善と強度の上昇に有効な元素であり、硫化水素分圧によらず耐SSCC性の向上に有効な元素である。本発明者らは、Moを含有する鋼板をSSCC試験に供した場合、試験後の鋼板表面は、Moを含有しない鋼板のSSCC試験後の表面に比べて平滑であることを知見した。そのメカニズムは必ずしも明確ではないが、このことが耐SSCC性の向上に関連すると考えられる。この効果を得るには0.01%以上を含有することが必要であり、0.10%以上を含有することが好ましい。一方で、含有量が多すぎると、焼入れ性が過剰になるため、加速冷却時に表層部や中心偏析部の硬さが上昇し、耐SSCC性が劣化する。また、溶接性も劣化する。このため、Mo量は0.50%以下とし、好ましくは0.40%以下とする。
Caは、硫化物系介在物の形態制御による耐HIC性向上に有効な元素であるが、0.0005%未満ではその添加効果が十分でない。このためCa量は0.0005%以上とし、好ましくは0.0008%以上とする。一方、0.0050%を超えた場合、上述の効果が飽和するだけでなく、鋼の清浄度が低下することにより耐HIC性が劣化するので、Ca量は0.0050%とし、好ましくは、0.0045%以下とする。
Cuは、靭性の改善と強度の上昇に有効な元素であり、この効果を得るには0.05%以上を含有することが好ましい。しかし、Cuは0.30%を超えて添加すると、1bar未満の硫化水素分圧の低い環境において、フィッシャーと呼ばれる微細割れが生成しやすくなるため、Cuを添加する場合は0.30%を上限とする。好ましくは、0.25%以下とする。
Niは、靭性の改善と強度の上昇に有効な元素であり、この効果を得るには0.01%以上を含有することが好ましい。しかし、Niは0.10%を超えて添加すると、1bar未満の硫化水素分圧の低い環境において、フィッシャーと呼ばれる微細割れが生成しやすくなるため、Niを添加する場合は0.10%を上限とする。好ましくは、0.02%以下とする。
Crは、Mnと同様、低Cでも十分な強度を得るために有効な元素であり、この効果を得るには0.05%以上を含有することが好ましい。しかし、含有量が多すぎると、焼入れ性が過剰になるため、加速冷却時に表層部や中心偏析部の硬さが上昇し、耐SSCC性が劣化する。また、溶接性も劣化する。このため、Crを添加する場合は0.50%を上限とする。好ましくは、0.45%以下とする。
CP=4.46[%C]+2.37[%Mn]/6+(1.74[%Cu]+1.7[%Ni])/15+(1.18[%Cr]+1.95[%Mo]+1.74[%V])/5+22.36[%P] ・・・(1)
ただし、[%X]はX元素の鋼中含有量(質量%)を示す。
次に、本開示の耐サワーラインパイプ用高強度鋼板の鋼組織について説明する。
鋼板表面下0.25mmの最高硬さを一定以下に抑え、耐SSCC性を向上させるために、鋼板表面下0.25mmの鋼組織を、ベイナイト組織とする必要がある。さらに、引張強さが520MPa以上の高強度化を図るために、鋼組織全体を、ベイナイト組織とすることが好ましい。特に、表層部は、マルテンサイトや島状マルテンサイト(MA)等の硬質相が生成した場合、表層硬さが上昇し、鋼板内の硬さのばらつきが増大して材質均一性が阻害される。表層硬さの上昇を抑制するために、表層部の鋼組織についてはベイナイト組織とする。
以下、上記耐サワーラインパイプ用高強度鋼板を製造するための製造方法および製造条件について、具体的に説明する。本開示の製造方法は、上記成分組成を有する鋼片を加熱したのち、熱間圧延して鋼板とし、その後当該鋼板に対して所定条件下での制御冷却を行う。
スラブ加熱温度:1000~1300℃
スラブ加熱温度が1000℃未満では、炭化物の固溶が不十分となり、固溶強化量が少なくなるため、必要な強度が得られない。一方1300℃を超えると、結晶粒が極端に粗大化し、靭性が劣化するため、スラブ加熱温度は1000~1300℃とする。好ましくは、1030~1250℃とする。なお、スラブは中心部までこの温度に加熱されるものとする。
熱間圧延工程において、高い母材靱性を得るには、圧延終了温度は低いほどよいが、その反面、圧延能率が低下するため、鋼板表面温度における圧延終了温度は、必要な母材靱性と圧延能率を勘案して設定する必要がある。強度および耐HIC性を向上させる観点からは、圧延終了温度を、鋼板表面温度でAr3変態点以上とすることが好ましい。ここで、Ar3変態点とは、冷却中におけるフェライト変態開始温度を意味し、例えば、鋼の成分から以下の式で求めることができる。なお、鋼板の表面温度は放射温度計等で測定することができる。
Ar3(℃)=910-310[%C]-80[%Mn]-20[%Cu]-15[%Cr]-55[%Ni]-80[%Mo]
ただし、[%X]はX元素の鋼中含有量(質量%)を示す。
冷却開始温度:鋼板表面温度で(Ar3-10℃)以上
冷却開始時の鋼板表面温度が低いと、制御冷却前のフェライト生成量が多くなる。特にAr3変態点からの温度降下量が10℃を超えた温度から冷却を開始すると体積分率で5%を超えるフェライトが生成して、強度低下が大きくなると共に耐HIC性が劣化する。このため、冷却開始時の鋼板表面温度は(Ar3-10℃)以上とする。
鋼板表面下0.25mmにおける硬さの上昇を抑えるためには、表層部の冷却速度を制御して、ベイナイト組織を制御することが重要である。
鋼板表面下0.25mmにおける鋼板温度で750℃から550℃までの平均冷却速度を極力遅くし、高温変態相を造り込むことが重要であり、冷却速度が遅くなるにつれ、最高硬さを低くすることができる。750℃から550℃までの温度域がベイナイト変態において重要な温度域となるので、この温度域における冷却速度を制御することが重要になる。冷却速度が50℃/s超では、低温変態相の割合が高く、鋼板表面下0.25mmでのHV0.5の最高硬さが230を超えるため、造管後の耐SSCC性が劣化する。そのため、当該平均冷却速度は50℃/s以下とする。好ましくは30℃/s以下である。当該平均冷却速度の下限は特に限定されないが、冷却速度が過度に小さくなるとフェライトやパーライトが生成して強度不足となるため、これを防ぐ観点から、20℃/s以上とすることが好ましい。なお、鋼板表面下0.25mmにおける鋼板温度で550℃以下の冷却については、冷却速度が遅い場合、安定した核沸騰状態での冷却にならず、鋼板の極表層部で硬さばらつきが生じ、ビッカース硬さの最高値が高くなる、おそれがあるため、鋼板表面下0.25mmにおける鋼板温度で550℃から冷却停止温度までの平均冷却速度は150℃/s以上が好ましい。
鋼板平均温度で750℃から550℃までの平均冷却速度が15℃/s未満では、ベイナイト組織が得られずに強度低下や耐HIC性の劣化が生じる。このため、鋼板平均温度での冷却速度は15℃/s以上とする。鋼板強度と硬さのばらつき抑制の観点からは、鋼板平均温度の冷却速度は20℃/s以上とすることが好ましい。当該平均冷却速度の上限は特に限定されないが、低温変態相が過剰に生成しないように、当該平均冷却速度は40℃/s以下とすることが好ましい。
冷却停止温度:鋼板表面下0.25mmにおける鋼板温度で250~550℃
冷却停止温度が550℃を超えると、ベイナイト変態が不完全になり、十分な強度が得られない。また、冷却停止温度が250℃未満では、転位密度が高くなるため、造管した際の表層部の硬さ上昇が著しくなり、耐SSCC性が劣化する。
本開示の高強度鋼板を、プレスベンド成形、ロール成形、UOE成形等で管状に成形した後、突き合わせ部を溶接することにより、原油や天然ガスの輸送に好適な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管(UOE鋼管、電縫鋼管、スパイラル鋼管等)を製造することができる。また、本開示の高強度鋼板を鋼管に用いることにより、溶接部の高硬度域が存在しても、耐SSCC性に優れる鋼管を製造することができる。
上記に従って得られた鋼板のミクロ組織を、光学顕微鏡および走査型電子顕微鏡により観察した。すなわち、鋼板の板幅中央部より金属組織観察用サンプルを採取し、このサンプルについて圧延長手方向と平行な断面を鏡面研磨したあと、ナイタールエッチングを行ってから、光学顕微鏡を用いて、400~1000倍の範囲の倍率で無作為に5視野写真撮影を行い、画像解析処理によって組織分率を算出した。鋼板表面下0.25mmの位置での組織と、板厚中央での組織を、表2に示す。さらに、鋼板表面下0.25mmの位置での組織をそれぞれ500μm×200μmの視野でEBSD(Electron Backscatter Diffraction)解析(測定ステップ:0.3μm)した。このEBSD解析の結果、5度以上の方位差を有する部分を粒界と判断して描出するBoundaryマップを作成した。また、EBSD解析の結果から、結晶粒内の各ピクセルと隣接するピクセルとの方位差の平均値であるKAM値を描出するKAMマップを作成した。得られたBoundaryマップとKAMマップを重ね合わせ、無作為に100個の結晶粒を選び、KAM値0.4以上のベイナイト面積率を測定した。これら測定の結果を表2に示す。
圧延方向に直角な方向の全厚試験片を引張試験片として引張試験を行い、引張強さおよび降伏強さを測定した。その結果を表2に示す。
圧延方向に直角な断面について、JIS Z 2244に準拠して、鋼管内表面下0.25mmの位置において100点のビッカース硬さ(HV0.5)を測定し、その最高硬さを求めた。最高硬さの値を表2に示す。ここで、通常用いられるHV10に代えてHV0.5で測定したのは、HV0.5で測定することにより圧痕が小さくなるので、より表面に近い位置での硬さ情報や、よりミクロ組織に敏感な硬さ情報を得ることが可能となるからである。HV0.5未満で測定すると、圧痕サイズが過度に小さく、測定ばらつきが大きくなる。また、平均硬さでなく最高硬さで評価する理由は、局所的に硬い箇所が存在すると、亀裂が進展しやすくなるからである。
耐SSCC性は、図1に示すように、得られた鋼管から切り出した試験片(クーポン; coupon)をフラットニングした後、5×15×115mmのSSCC試験片を鋼管内面より採取した。このとき、溶接部を含まない母材だけの試験片のほかに、溶接部と母材の両方を含む試験片を採取した。被検面である内面は、最表層の状態を残すために黒皮付きのままとした。すなわち、鋼板表面下0.25mmは試験片に含まれている。かくして採取したSSCC試験片に、各鋼管の実際の降伏強度(0.5%YS)の90%の応力を負荷し、NACE規格 TM0177 Solution A溶液を用い、硫化水素分圧:1barにて、EFC16規格の4点曲げSSCC試験に準拠して行った。また、同様にNACE規格 TM0177 Solution B溶液を用い、硫化水素分圧:0.1bar+二酸化炭素分圧:0.9barにて、EFC16規格の4点曲げSSCC試験に準拠して行った。さらに、NACE規格 TM0177 Solution A溶液を用い、硫化水素分圧:2bar+二酸化炭素分圧:3barについても、EFC16規格の4点曲げSSCC試験に準拠して行った。720時間の浸漬後に、溶接部を含まない母材だけの試験片と、溶接部と母材の両方を含む試験片との両方において、割れが認められない場合を耐SSCC性が良好と判断して○、また少なくとも一方の試験片において割れが発生した場合を不良と判断して×とした。結果を表2に示す。
耐HIC性は、NACE規格 TM0177 Solution A溶液を用い、硫化水素分圧:1barにて、96時間浸漬のHIC試験により調べた。また、NACE規格 TM0177 Solution B溶液を用い、硫化水素分圧:0.1bar+二酸化炭素分圧:0.9barにて、96時間浸漬のHIC試験により調べた。耐HIC性は、HIC試験で割れ長さ率(CLR)が10%以下となった場合を優秀と判断して◎、15%以下となった場合を良好と判断して○、15%を超えた場合を×とした。結果を表2に示す。
Claims (5)
- 質量%で、C:0.020~0.080%、Si:0.01~0.50%、Mn:0.50~1.80%、P:0.015%以下、S:0.0015%以下、Al:0.010~0.080%、N:0.0010~0.0080%、Mo:0.01~0.50%およびCa:0.0005~0.0050%を含有し、残部がFeおよび不可避的不純物である成分組成を有し、
鋼板表面下0.25mmにおける鋼組織がベイナイト組織であり、当該ベイナイトにおける、KAM(Kernel Average Misorientation)値が0.4以上である結晶粒の面積率が50%以下であり、
鋼板表面下0.25mmにおけるビッカース硬さの最高値が230Hv以下であり、
引張強さが520MPa以上である耐サワーラインパイプ用高強度鋼板。 - 前記成分組成が、さらに、質量%で、Cu:0.30%以下、Ni:0.10%以下およびCr:0.50%以下のうちから選んだ1種以上を含有する、請求項1に記載の耐サワーラインパイプ用高強度鋼板。
- 前記成分組成が、さらに、質量%で、Nb:0.005~0.1%、V:0.005~0.1%、Ti:0.005~0.1%、Zr:0.0005~0.02%、Mg:0.0005~0.02%、およびREM:0.0005~0.02%のうちから選んだ1種以上を含有する、請求項1または2に記載の耐サワーラインパイプ用高強度鋼板。
- 請求項1、2または3に記載の成分組成を有する鋼片を、1000~1300℃の温度に加熱したのち、熱間圧延して鋼板とし、
その後前記鋼板に対して、
冷却開始時の鋼板表面温度:(Ar3-10℃)以上、
鋼板表面下0.25mmにおける鋼板温度で750℃から550℃までの平均冷却速度:20~50℃/s、
鋼板平均温度で750℃から550℃までの平均冷却速度:15℃/s以上および
鋼板表面下0.25mmにおける鋼板温度で冷却停止温度:250~550℃
の条件で冷却を行う耐サワーラインパイプ用高強度鋼板の製造方法。 - 請求項1から3のいずれか一項に記載の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。
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Cited By (3)
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WO2023248638A1 (ja) * | 2022-06-21 | 2023-12-28 | 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及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 |
WO2024014098A1 (ja) * | 2022-07-14 | 2024-01-18 | Jfeスチール株式会社 | 水素輸送鋼管用高強度鋼板及びその製造方法並びに水素輸送用鋼管 |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0160297B2 (ja) * | 1978-11-15 | 1989-12-21 | Metarurujiiku Ru Nitsukeru Esu Eru Enu Soc | |
JP2011017048A (ja) | 2009-07-08 | 2011-01-27 | Nippon Steel Corp | 耐サワーラインパイプ用電縫鋼管の製造方法 |
WO2016056216A1 (ja) * | 2014-10-07 | 2016-04-14 | Jfeスチール株式会社 | ラインパイプ用鋼板及びその製造方法とラインパイプ用鋼管 |
JP6369658B1 (ja) | 2017-09-19 | 2018-08-08 | 新日鐵住金株式会社 | 鋼管及び鋼板 |
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 (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
RU2481415C2 (ru) * | 2007-11-07 | 2013-05-10 | ДжФЕ СТИЛ КОРПОРЕЙШН | Стальной лист и стальная труба для трубопроводов |
JP5672916B2 (ja) * | 2010-09-30 | 2015-02-18 | 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 |
JP5565420B2 (ja) * | 2012-02-02 | 2014-08-06 | 新日鐵住金株式会社 | ラインパイプ用uoe鋼管 |
KR101757710B1 (ko) * | 2012-07-09 | 2017-07-14 | 제이에프이 스틸 가부시키가이샤 | 후육 고강도 내사우어 라인 파이프의 제조 방법 |
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Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0160297B2 (ja) * | 1978-11-15 | 1989-12-21 | Metarurujiiku Ru Nitsukeru Esu Eru Enu Soc | |
JP2011017048A (ja) | 2009-07-08 | 2011-01-27 | Nippon Steel Corp | 耐サワーラインパイプ用電縫鋼管の製造方法 |
WO2016056216A1 (ja) * | 2014-10-07 | 2016-04-14 | Jfeスチール株式会社 | ラインパイプ用鋼板及びその製造方法とラインパイプ用鋼管 |
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 |
JP6369658B1 (ja) | 2017-09-19 | 2018-08-08 | 新日鐵住金株式会社 | 鋼管及び鋼板 |
Non-Patent Citations (1)
Title |
---|
See also references of EP4006180A4 |
Cited By (4)
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JP7396551B1 (ja) | 2022-06-21 | 2023-12-12 | 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及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 |
WO2023248638A1 (ja) * | 2022-06-21 | 2023-12-28 | 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及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 |
WO2024014098A1 (ja) * | 2022-07-14 | 2024-01-18 | Jfeスチール株式会社 | 水素輸送鋼管用高強度鋼板及びその製造方法並びに水素輸送用鋼管 |
JP7424550B1 (ja) | 2022-07-14 | 2024-01-30 | Jfeスチール株式会社 | 水素輸送鋼管用高強度鋼板及びその製造方法並びに水素輸送用鋼管 |
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EP4006180A1 (en) | 2022-06-01 |
KR20220032115A (ko) | 2022-03-15 |
JP7272442B2 (ja) | 2023-05-12 |
EP4006180A4 (en) | 2022-10-12 |
CN114174547A (zh) | 2022-03-11 |
JPWO2021020220A1 (ja) | 2021-02-04 |
BR112022001623A2 (pt) | 2022-03-22 |
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