WO2018181564A1 - High strength steel sheet for sour-resistant line pipe, method for manufacturing same, and high strength steel pipe using high strength steel sheet for sour-resistant line pipe - Google Patents
High strength steel sheet for sour-resistant line pipe, method for manufacturing same, and high strength steel pipe using high strength steel sheet for sour-resistant line pipe Download PDFInfo
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- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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Definitions
- the present invention is suitable for use in line pipes in the fields of architecture, offshore structures, shipbuilding, civil engineering, and construction industrial machines, and is a high-strength steel sheet for sour-resistant pipes with excellent material uniformity in the steel sheet and its manufacture. It is about the method.
- the present invention also relates to a high-strength steel pipe using the above-described high-strength steel plate for sour line pipes.
- 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 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 from the corrosion reaction are adsorbed on the steel surface, penetrate into the steel as atomic hydrogen, and diffuse and accumulate around non-metallic inclusions such as MnS and hard second-phase structures in the steel.
- TMCP Thermo-Mechanical Control Process
- TMCP Thermo-Mechanical Control Process
- it is effective to increase the cooling rate during controlled cooling.
- controlled cooling is performed at a high cooling rate, 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 plate, and the hardness distribution in the thickness direction varies. Therefore, it becomes a problem from the viewpoint of ensuring the material uniformity in the steel plate.
- Patent Documents 1 and 2 there is a material difference in the plate thickness direction by interrupting accelerated cooling after rolling, reaccelerating the surface, and then performing accelerated cooling again.
- a method for manufacturing a small steel sheet is disclosed.
- Patent Documents 3 and 4 disclose a method for manufacturing a steel plate for a line pipe, which uses a high-frequency induction heating device to heat the steel plate surface after accelerated cooling to a higher temperature from the inside to reduce the hardness of the surface layer portion. Has been.
- Patent Documents 5 and 6 disclose a method for improving the steel plate shape by reducing the uneven cooling due to the uneven thickness of the scale by performing descaling immediately before the cooling.
- Japanese Patent No. 3951428 Japanese Patent No. 3951429 JP 2002-327212 A Japanese Patent No. 3711896 JP-A-9-57327 Japanese Patent No. 3796133
- Patent Documents 5 and 6 improve the steel sheet shape by descaling to reduce surface quality defects due to indentation of the scale during hot correction and to reduce variation in the cooling stop temperature of the steel sheet.
- the cooling conditions for obtaining a uniform material no consideration is given to the cooling conditions for obtaining a uniform material. That is, in the techniques described in Patent Documents 5 and 6, the cooling rate of the surface layer portion in the accelerated cooling is not considered at all. Therefore, there is a possibility that the hardness of the surface layer portion may not be sufficiently reduced at the cooling rate for securing the tensile properties in the center of the plate thickness, and as a result, the hardness may vary in the plate thickness direction. Concerned.
- the present invention provides a high-strength steel sheet for sour line pipes that is excellent in HIC resistance and SSCC resistance under a more severe corrosive environment and excellent in hardness uniformity in the thickness direction. It is intended to provide with its advantageous manufacturing method.
- Another object of the present invention is to propose a high-strength steel pipe using the high-strength steel sheet for sour-resistant pipes.
- the present inventors repeated numerous experiments and examinations on the component composition, microstructure, and production conditions of the steel material in order to ensure HIC resistance and SSCC resistance under a more severe corrosive environment.
- the structure of the extreme surface layer portion of the steel sheet specifically the steel sheet surface
- an increase in hardness can be reduced in the coating process after pipe forming. It was found that the SSCC resistance of the steel pipe was improved as a result.
- both the thermal history at 0.5 mm below the steel sheet surface in the controlled cooling and the thermal history of the steel sheet average are strictly controlled, and then the excess introduced by the controlled cooling.
- by performing induction heating under a predetermined condition in consideration of the steel plate surface temperature T 1 at the start of cooling in the controlled cooling and the cooling stop temperature T 2 at the steel plate average temperature the variation in hardness in the plate thickness direction is caused. It was found that it can be significantly reduced.
- the present invention has been made based on this finding.
- the gist configuration of the present invention is as follows. [1] By 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% and Ca: 0.0005 to 0.005%, and the CP value obtained by the following formula (1) is 1 0.000 or less, and the balance has a component composition consisting of Fe and inevitable impurities,
- the steel structure at 0.5 mm below the steel sheet surface is a bainite structure having a dislocation density of 0.5 ⁇ 10 14 to 7.0 ⁇ 10 14 (m ⁇ 2 ),
- the difference ⁇ HV between the average value of Vickers hardness at 0.5 mm below the steel sheet surface and the average value of Vickers hardness at the center of the steel sheet thickness is 25 HV or less,
- the component composition was further selected by mass% from Cu: 0.50% or less, Ni: 0.50% or less, Cr: 0.50% or less, and Mo: 0.50% or less.
- the component composition is further selected from Nb: 0.005 to 0.1%, V: 0.005 to 0.1%, and Ti: 0.005 to 0.1% by mass%.
- the component composition is further selected by mass% from Cu: 0.50% or less, Ni: 0.50% or less, Cr: 0.50% or less, and Mo: 0.50% or less.
- the component composition is further selected from Nb: 0.005 to 0.1%, V: 0.005 to 0.1% and Ti: 0.005 to 0.1% by mass%.
- TP (T 3 ⁇ T 2 ) ⁇ T 2 / (T 1 ⁇ T 2 ) 2 (2)
- the high-strength steel plate for sour line pipe and the high-strength steel pipe using the high-strength steel plate for sour line pipe of the present invention are excellent in HIC resistance and SSCC resistance in a more severe corrosion environment, and in the thickness direction. Excellent hardness uniformity. Further, according to the method for producing a high-strength steel sheet for sour line pipes of the present invention, the HIC resistance and SSCC resistance in a more severe corrosive environment are excellent, and the hardness uniformity in the thickness direction is also excellent.
- a high-strength steel sheet for sour line pipes can be manufactured.
- C 0.02 to 0.08% C contributes effectively to the improvement of strength, but if the content is less than 0.02%, sufficient strength cannot be secured, while if it exceeds 0.08%, the hardness of the surface layer portion increases during accelerated cooling. , HIC resistance and SSCC resistance deteriorate. In addition, toughness deteriorates. For this reason, the C content is limited to a 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 deoxidation effect is not sufficient. On the other hand, if it exceeds 0.50%, the toughness and weldability are deteriorated. It is limited to the range of 01 to 0.50%.
- Mn 0.50 to 1.80% Mn contributes effectively to the improvement of strength and toughness, but if the content is less than 0.50%, the effect of addition is poor, while if it exceeds 1.80%, the hardness of the central segregation part increases during accelerated cooling. Therefore, the HIC resistance is deteriorated. Moreover, weldability also deteriorates. For this reason, the amount of Mn is limited to the range of 0.50 to 1.80%.
- P 0.001 to 0.015%
- P is an inevitable impurity element, and deteriorates the weldability and also increases the hardness of the center segregation part to deteriorate the HIC resistance. Since the tendency will become remarkable when it exceeds 0.015%, an upper limit is prescribed
- S 0.0002 to 0.0015%
- S is an unavoidable impurity element, and is preferably MnS inclusion in the steel, so that the HIC resistance is degraded. The lower the content, the better, but 0.0002% or more from the viewpoint of refining costs.
- Al 0.01 to 0.08% Al is added as a deoxidizer, but if it is less than 0.01%, there is no effect of addition. On the other hand, if it exceeds 0.08%, the cleanliness of the steel is lowered and the toughness is deteriorated. It is limited to the range of 01 to 0.08%.
- Ca 0.0005 to 0.005%
- Ca is an element effective for improving the HIC resistance by controlling the form of sulfide inclusions, but if it is less than 0.0005%, the effect of addition is not sufficient. On the other hand, if it 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, so the Ca content is limited to the range of 0.0005 to 0.005%. .
- the component composition of the present disclosure may be one or more selected from Cu, Ni, Cr, and Mo in order to further improve the strength and toughness of the steel sheet. Can be optionally contained within the following range.
- 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, but if the content is too large, welding is performed. When Cu is added, the upper limit is 0.50%.
- Ni 0.50% or less
- Ni is an element effective for improving toughness and increasing strength. To obtain this effect, it is preferable to contain 0.05% or more, but if the content is too large, it is economical. This is not only disadvantageous, but also the toughness of the weld heat affected zone deteriorates. Therefore, when Ni is added, the upper limit is 0.50%.
- Cr 0.50% or less Cr, like Mn, is an element effective for obtaining sufficient strength even at low C. To obtain this effect, it is preferable to contain 0.05% or more. If the amount is too large, weldability deteriorates, so when Cr is added, the upper limit is 0.50%.
- Mo 0.50% or less Mo is an element effective in improving toughness and increasing strength. To obtain this effect, it is preferable to contain 0.05% or more, but if the content is too large, welding is performed. When the Mo is added, the upper limit is 0.50%.
- the component composition of the present disclosure may further contain one or more selected from Nb, V and Ti within the following ranges.
- Nb 0.005 to 0.1%
- V 0.005 to 0.1%
- Ti 0.005 to 0.1%
- Any of Nb, V and Ti Is an element that can be optionally added to increase the strength and toughness of the steel sheet.
- the content of each element is less than 0.005%, the effect of addition is poor.
- the content exceeds 0.1% the toughness of the welded portion deteriorates. It is preferable to be in the range.
- This disclosure discloses a technique for improving the SSCC resistance of a high-strength steel pipe using a high-strength steel plate for sour line pipes.
- the sour-proof performance is not limited to HIC resistance. Since it is necessary to satisfy simultaneously, CP value calculated
- the CP value is an expression devised for estimating the material of the center segregation part from the content of each alloy element.
- the higher the CP value of the above formula (1) the higher the component concentration of the center segregation part. Increases and the hardness of the central segregation part increases. Therefore, it is possible to suppress the occurrence of cracks in the HIC test by setting the CP value obtained in the above equation (1) to 1.00 or less. Further, the lower the CP value, the lower the hardness of the center segregation part. Therefore, when higher HIC resistance is required, the upper limit may be set to 0.95.
- the steel structure of the high-strength steel sheet for sour line pipes In order to increase the tensile strength of 520 MPa or more, the steel structure needs to be a bainite structure.
- a hard phase such as martensite or island martensite (MA)
- the surface layer hardness is increased, the hardness variation in the steel sheet is increased, and the material uniformity is inhibited.
- the steel structure of the surface layer portion is a bainite structure.
- the bainite structure includes a structure called bainitic ferrite or granular ferrite that transforms during or after accelerated cooling that contributes to transformation strengthening.
- bainitic ferrite or granular ferrite that transforms during or after accelerated cooling that contributes to transformation strengthening.
- different types of structures such as ferrite, martensite, pearlite, island-like martensite, and retained austenite
- the strength decreases, the toughness deteriorates, and the surface hardness increases.
- the smaller the fraction the better.
- the volume fraction of the structure other than the bainite phase is sufficiently low, the influence thereof can be ignored, so that a certain amount is acceptable.
- the structure of the extreme surface layer portion of the steel sheet specifically, the steel structure of 0.5 mm below the steel sheet surface has a dislocation density of 0. It is important to have a bainite structure of 5 ⁇ 10 14 to 7.0 ⁇ 10 14 (m ⁇ 2 ). Since the dislocation density decreases in the coating process after pipe forming, if the dislocation density 0.5 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. To the limit.
- dislocation density of 0.5 mm below the steel sheet surface exceeds 7.0 ⁇ 10 14 (m ⁇ 2 )
- the dislocation density does not decrease in the coating process after pipe forming, and the hardness increases greatly by age hardening.
- a preferable range of dislocation density is 6.0 ⁇ 10 14 (m ⁇ 2 ) or less.
- the dislocation density 0.5 mm below the steel sheet surface is less than 0.5 ⁇ 10 14 (m ⁇ 2 )
- the strength of the steel sheet cannot be maintained.
- the dislocation density in the steel structure 0.5 mm below the steel sheet surface is in the above range, the extreme surface layer part in the range of 0.5 mm depth from the steel sheet surface also has an equivalent dislocation density. As a result, the effect of improving the SSCC resistance can be obtained.
- the HV0.1 at 0.5 mm below the surface is 230 or less. From the viewpoint of securing the SSCC resistance of the steel pipe, it is important to suppress the surface hardness of the steel sheet. However, by setting the HV0.1 at 0.5 mm below the surface of the steel sheet to 230 or less, coating after pipe forming After the process, HV0.1 at 0.5 mm below the surface can be suppressed to 260 or less, and SSCC resistance can be ensured.
- the material properties at the center of the sheet thickness can be secured while suppressing the hardness of the surface layer.
- the difference ⁇ HV between the average value of Vickers hardness at 0.5 mm below the steel sheet surface and the average value of Vickers hardness at the center of the steel sheet thickness is 25 HV or less. More preferable ⁇ HV is 20 HV or less.
- the high-strength steel sheet of the present disclosure is a steel pipe steel sheet having an API 5L X60 grade or higher strength, it has 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 required strength cannot be obtained due to insufficient solid solution of the carbide. On the other hand, if the slab heating temperature exceeds 1300 ° C., the toughness deteriorates, so the slab heating temperature is set to 1000 to 1300 ° C. This temperature is the furnace temperature of the heating furnace, and 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 strength and HIC resistance, it is preferable that the rolling end temperature is not less 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 steel components by the following formula, for example.
- austenite non-recrystallization temperature range be 60% or more.
- surface temperature of a steel plate 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 element X in steel.
- Average cooling rate from 750 ° C. to 550 ° C. at a steel plate temperature at 0.5 mm below the steel plate surface 100 ° C./s or less Average cooling rate from 750 ° C. to 550 ° C. at a steel plate temperature at 0.5 mm below the steel plate surface is 100 ° C. / If it exceeds s, the dislocation density at 0.5 mm below the steel sheet surface exceeds 7.0 ⁇ 10 14 (m ⁇ 2 ). As a result, HV0.1 of 0.5 mm below the steel sheet surface exceeds 230, and after passing through the coating process after pipe forming, HV0.1 at 0.5 mm below the surface exceeds 260, and the SSCC resistance of the steel pipe deteriorates. To do.
- the said average cooling rate shall be 100 degrees C / s or less. Preferably it is 80 degrees C / s or less.
- the lower limit of the average cooling rate is not particularly limited. However, if the cooling rate is excessively small, ferrite and pearlite are generated and the strength becomes insufficient. Therefore, from the viewpoint of preventing this, it is preferably set to 10 ° C./s or more.
- Average cooling rate from 750 ° C. to 550 ° C. at the average temperature of the steel plate 15 ° C./s or more
- the average cooling rate from 750 ° C. to 550 ° C. at the average temperature of the steel plate is less than 15 ° C./s, the bainite structure is not obtained and the strength Decrease and deterioration of HIC resistance occur, or the variation in hardness in the thickness direction increases.
- the cooling rate at the steel plate average temperature is set to 15 ° C./s or more.
- the average cooling rate of the steel plate is preferably 20 ° C./s or more.
- the upper limit of the average cooling rate is not particularly limited, but is preferably set to 80 ° C./s or less so that the low temperature transformation product is not excessively generated.
- the 0.5 mm below the steel plate surface and the average steel plate temperature cannot be physically measured directly, but the surface temperature at the start of cooling measured with a radiation thermometer and the surface temperature at the target cooling stop are also measured.
- the temperature distribution in the cross section of the plate thickness can be obtained in real time by difference calculation using a process computer.
- the temperature at 0.5 mm below the steel sheet surface in the temperature distribution is defined as “steel temperature at 0.5 mm below the steel sheet surface” in this specification, and the average value of the temperature in the plate thickness direction in the temperature distribution is “ Average temperature ”.
- Induction heating temperature T 3 550 to 750 ° C. at the steel sheet surface temperature
- the dislocation density at 0.5 mm below the steel sheet surface was 7.0 ⁇ 10 14 (m ⁇ 2 ) or less, and excellent SSCC resistance was obtained, and the average of the Vickers hardness at 0.5 mm below the steel sheet surface was obtained.
- the difference ⁇ HV between the value and the average value of Vickers hardness at the center of the steel plate thickness can be 25 HV or less.
- the induction heating temperature is lower than 550 ° C., a sufficient tempering effect cannot be obtained, and even if the dislocation density of the surface layer can be 7.0 ⁇ 10 14 (m ⁇ 2 ) or less, ⁇ HV is It cannot be less than 25HV.
- the induction heating temperature exceeds 750 ° C., the center of the plate thickness is also tempered, and there is a possibility that a predetermined strength cannot be obtained. Therefore, in order to secure the strength at the center of the plate thickness while suppressing deterioration of material uniformity in the steel plate, the ultimate temperature of the on-line induction heating is set to 550 to 750 ° C. at the steel plate surface temperature. In the present embodiment, it is important that only the surface layer portion is tempered without tempering the inside of the steel sheet as much as possible in order to suppress a decrease in strength, and therefore, an online induction heating device is used for heating.
- TP defined by the following formula (2) satisfies 0.50 or more and 1.50 or less. More preferably, it is 0.60 or more and 1.00 or less.
- TP (T 3 ⁇ T 2 ) ⁇ T 2 / (T 1 ⁇ T 2 ) 2 (2)
- TP is a relational expression of tempering with respect to the degree of supercooling of the controlled cooling, and when this satisfies 0.50 or more, the dislocation of the surface layer portion introduced by the accelerated cooling is sufficiently recovered and excessive in the center of the plate thickness. Since tempering is not imitated, it is possible to remarkably suppress variation in hardness in the thickness direction. Specifically, ⁇ HV can be set to 20 or less.
- 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, ERW steel pipes, spiral steel pipes, etc. can be manufactured.
- the end of a steel plate is grooved and 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.
- Any welding method may be used as long as sufficient joint strength and joint toughness can be obtained, but it is preferable to use submerged arc welding from the viewpoint of excellent welding quality and manufacturing efficiency.
- Steels (steel types A to I) having the composition shown in Table 1 were made into slabs by a continuous casting method, heated to the temperatures shown in Table 2, and then hot rolled at the rolling end temperatures and reduction rates shown in Table 2. Thus, a steel plate having a thickness shown in Table 2 was obtained. Thereafter, controlled cooling was performed on the steel sheet using a water-cooled control cooling device under the conditions shown in Table 2. Immediately thereafter, the steel sheet was reheated by the method shown in “Heating Method” in Table 2 so that the steel sheet surface temperature became the “maximum temperature during reheating” in Table 2.
- Dislocation density A sample for X-ray diffraction was collected from a position having an average hardness, the sample surface was polished to remove the scale, and X-ray diffraction measurement was performed at a position 0.5 mm below the steel sheet surface. The dislocation density was converted from the strain obtained from the half width ⁇ of the X-ray diffraction measurement. In the diffraction intensity curve obtained by normal X-ray diffraction, the K ⁇ 1 line and the K ⁇ 2 line having different wavelengths overlap each other, so that they are separated by the Rachinger method. The Williamsson-Hall method shown below is used for distortion extraction.
- the spread of the half width is affected by the size D of the crystallite and the strain ⁇ , and can be calculated by the following equation as the sum of both factors.
- ⁇ 14.4 ⁇ 2 / b 2
- ⁇ means the peak angle calculated by the ⁇ -2 ⁇ method of X-ray diffraction
- ⁇ means the wavelength of X-rays used in X-ray diffraction
- b is a Burgers vector of Fe ( ⁇ ), and in this example, it was 0.25 nm.
- SSCC resistance was evaluated by pipe forming using a part of each of these steel plates. Pipe making is performed after the end of the steel plate is grooved and formed into a steel pipe shape by C-press, U-press and O-press, then the butt part of the inner and outer surfaces is seam welded by submerged arc welding, and the tube is expanded. did. As shown in FIG. 1, after flattening a coupon cut out from the obtained steel pipe, 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 test surface, was left with a black skin to leave the outermost layer.
- the collected SSCC test piece was loaded with 90% of the actual yield strength (0.5% YS) of each steel pipe, and using NACE TM0177 Solution A solution, hydrogen sulfide partial pressure: 1 bar, EFC16 standard
- NACE TM0177 Solution A solution, hydrogen sulfide partial pressure: 1 bar, EFC16 standard The four-point bending SSCC test was conducted. A case where no crack was observed after immersing for 720 hours was judged as good when the SSCC resistance was good, and a case where a crack occurred was judged as poor and was marked as x.
- Table 2 The results are shown in Table 2.
- HIC resistance was evaluated as “Good” when a HIC test was conducted with an immersion time of 96 hours in accordance with NACE Standard TM-02-84. As evaluated. The results are shown in Table 2.
- the target range of the present invention is that the tensile strength is 520 MPa or more as a high-strength steel plate for sour line pipes, the microstructure is a bainite structure at 0.5 mm below the surface and the t / 2 position, and HV0.1 is 0.5 mm below the surface. Is 230 or less, the absolute value ⁇ HV of the difference between the hardness at 0.5 mm below the surface and the hardness at the center of the plate thickness is 25 or less, and no cracks are observed in the SSCC test in a high-strength steel pipe made using the steel plate In addition, no cracks were observed in the HIC test.
- No. 1-No. 9 is an invention example 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 0.5 mm position and the t / 2 position below the surface
- the HV0.1 is 0.5 or less
- the ⁇ HV is 25 or less at 0.5 mm below the surface
- SSCC resistance and HIC resistance were also good in the high-strength steel pipe made using the steel plate.
- No. 10-No. No. 16 is a comparative example in which the component composition is within the scope of the present invention but the production conditions are outside the scope of the present invention.
- the cooling stop temperature was low, so the difference in hardness between the surface layer and the center of the plate thickness was large.
- the controlled cooling condition was outside the range of the present invention, and the dislocation density was significantly increased in the steel sheet surface layer, so that the surface layer hardness increased and SSCC was generated.
- No. 13 the average cooling rate of the steel plate was not sufficiently secured, and ferrite was formed at the center of the plate thickness. In No.
- the heating temperature in the on-line induction heating was not optimal, so that a hardness difference in the plate thickness direction occurred.
- No. No. 15 is tempered by furnace heating, but has a low strength because the rate of temperature rise is slow and the entire thickness is tempered on average.
- No. No. 16 is a case in which reheating is not performed, and since the surface layer is not softened by tempering, the dislocation density of the surface layer is high, which causes the occurrence of SSCC. Also, the thickness variation in the thickness direction is large.
- the component composition of the steel sheet is outside the scope of the present invention, and the HIC resistance is deteriorated.
- a steel pipe (such as an electric resistance steel pipe, a spiral steel pipe, or a UOE steel pipe) manufactured by cold forming this steel sheet can be suitably used for transporting crude oil or natural gas containing hydrogen sulfide that requires sour resistance. .
Abstract
Description
[1]質量%で、C:0.02~0.08%、Si:0.01~0.50%、Mn:0.50~1.80%、P:0.001~0.015%、S:0.0002~0.0015%、Al:0.01~0.08%およびCa:0.0005~0.005%を含有し、以下の式(1)によって求められるCP値が1.00以下となり、残部がFeおよび不可避的不純物からなる成分組成を有し、
鋼板表面下0.5mmにおける鋼組織が、転位密度0.5×1014~7.0×1014(m-2)のベイナイト組織であり、
鋼板表面下0.5mmにおけるビッカース硬さの平均値と鋼板板厚中央におけるビッカース硬さの平均値との差ΔHVが25HV以下であり、
520MPa以上の引張強さを有する
ことを特徴とする耐サワーラインパイプ用高強度鋼板。
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。 That is, the gist configuration of the present invention is as follows.
[1] By 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% and Ca: 0.0005 to 0.005%, and the CP value obtained by the following formula (1) is 1 0.000 or less, and the balance has a component composition consisting of Fe and inevitable impurities,
The steel structure at 0.5 mm below the steel sheet surface is a bainite structure having a dislocation density of 0.5 × 10 14 to 7.0 × 10 14 (m −2 ),
The difference ΔHV between the average value of Vickers hardness at 0.5 mm below the steel sheet surface and the average value of Vickers hardness at the center of the steel sheet thickness is 25 HV or less,
A high-strength steel sheet for sour line pipes, characterized by having a tensile strength of 520 MPa or more.
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)
However, [% X] indicates the content (mass%) of element X in steel.
その後前記鋼板に対して、
冷却開始時の鋼板表面温度T1:(Ar3-10℃)以上、
鋼板表面下0.5mmにおける鋼板温度で750℃から550℃までの平均冷却速度:100℃/s以下、
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
鋼板平均温度で冷却停止温度T2:250~550℃
の条件で制御冷却を行い、
その後、誘導加熱により、鋼板平均温度が前記冷却停止温度T2以上であって、かつ鋼板表面温度が550~750℃の加熱温度T3となるように前記鋼板を再加熱することを特徴とする耐サワーラインパイプ用高強度鋼板の製造方法。
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。 [4] By 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% and Ca: 0.0005 to 0.005%, and the CP value obtained by the following formula (1) is 1 A steel slab having a component composition of Fe and unavoidable impurities in the balance is heated to 1000-1300 ° C., and then hot-rolled into a steel plate,
After that,
Steel sheet surface temperature T 1 at the start of cooling: (Ar 3 −10 ° C.) or more,
Average cooling rate from 750 ° C. to 550 ° C. at a steel plate temperature at 0.5 mm below the steel plate surface: 100 ° C./s or less,
Average cooling rate from 750 ° C. to 550 ° C. at the steel plate average temperature: 15 ° C./s or more, and cooling stop temperature T 2 at the steel plate average temperature: 250 to 550 ° C.
Controlled cooling under the conditions of
Thereafter, the steel sheet is reheated by induction heating so that the average temperature of the steel sheet is equal to or higher than the cooling stop temperature T 2 and the steel sheet surface temperature is a heating temperature T 3 of 550 to 750 ° C. Manufacturing method of high strength steel plate for sour line pipes.
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)
However, [% X] indicates the content (mass%) of element X in steel.
TP=(T3-T2)×T2/(T1-T2)2 ・・・(2) [7] The reheating is performed so as to satisfy a condition that a TP defined by the following formula (2) is 0.50 or more, according to any one of the above [4] to [6]. Manufacturing method of high strength steel plate for sour line pipe.
TP = (T 3 −T 2 ) × T 2 / (T 1 −T 2 ) 2 (2)
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%で示す単位は全て質量%である。 [Ingredient composition]
First, the component composition of the high-strength steel sheet according to the present disclosure and the reason for limitation will be described. In the following description, all units represented by% are mass%.
Cは、強度の向上に有効に寄与するが、含有量が0.02%未満では十分な強度が確保できず、一方0.08%を超えると加速冷却時に表層部の硬さが上昇するため、耐HIC性および耐SSCC性が劣化する。また、靭性も劣化する。このため、C量は0.02~0.08%の範囲に限定する。 C: 0.02 to 0.08%
C contributes effectively to the improvement of strength, but if the content is less than 0.02%, sufficient strength cannot be secured, while if it exceeds 0.08%, the hardness of the surface layer portion increases during accelerated cooling. , HIC resistance and SSCC resistance deteriorate. In addition, toughness deteriorates. For this reason, the C content is limited to a range of 0.02 to 0.08%.
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く、一方0.50%を超えると靭性や溶接性を劣化させるため、Si量は0.01~0.50%の範囲に限定する。 Si: 0.01 to 0.50%
Si is added for deoxidation, but if the content is less than 0.01%, the deoxidation effect is not sufficient. On the other hand, if it exceeds 0.50%, the toughness and weldability are deteriorated. It is limited to the range of 01 to 0.50%.
Mnは、強度、靭性の向上に有効に寄与するが、含有量が0.50%未満ではその添加効果に乏しく、一方1.80%を超えると加速冷却時に中心偏析部の硬さが上昇するため、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0.50~1.80%の範囲に限定する。 Mn: 0.50 to 1.80%
Mn contributes effectively to the improvement of strength and toughness, but if the content is less than 0.50%, the effect of addition is poor, while if it exceeds 1.80%, the hardness of the central segregation part increases during accelerated cooling. Therefore, the HIC resistance is deteriorated. Moreover, weldability also deteriorates. For this reason, the amount of Mn is limited to the range of 0.50 to 1.80%.
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、中心偏析部の硬さを上昇させることで耐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%に規定する。好ましくは0.008%以下である。含有量は低いほどよいが、精錬コストの観点から0.001%以上とする。 P: 0.001 to 0.015%
P is an inevitable impurity element, and deteriorates the weldability and also increases the hardness of the center segregation part to deteriorate the HIC resistance. Since the tendency will become remarkable when it exceeds 0.015%, an upper limit is prescribed | regulated to 0.015%. Preferably it is 0.008% or less. The lower the content, the better, but 0.001% or more from the viewpoint of refining costs.
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%までは許容される。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。 S: 0.0002 to 0.0015%
S is an unavoidable impurity element, and is preferably MnS inclusion in the steel, so that the HIC resistance is degraded. The lower the content, the better, but 0.0002% or more from the viewpoint of refining costs.
Alは、脱酸剤として添加するが、0.01%未満では添加効果がなく、一方、0.08%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0.01~0.08%の範囲に限定する。 Al: 0.01 to 0.08%
Al is added as a deoxidizer, but if it is less than 0.01%, there is no effect of addition. On the other hand, if it exceeds 0.08%, the cleanliness of the steel is lowered and the toughness is deteriorated. It is limited to the range of 01 to 0.08%.
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。一方、0.005%を超えた場合、効果が飽和するだけでなく、鋼の清浄度の低下により耐HIC性を劣化させるので、Ca量は0.0005~0.005%の範囲に限定する。 Ca: 0.0005 to 0.005%
Ca is an element effective for improving the HIC resistance by controlling the form of sulfide inclusions, but if it is less than 0.0005%, the effect of addition is not sufficient. On the other hand, if it 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, so the Ca content is limited to the range of 0.0005 to 0.005%. .
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が、含有量が多すぎると溶接性が劣化するため、Cuを添加する場合は0.50%を上限とする。 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, but if the content is too large, welding is performed. When Cu is added, the upper limit is 0.50%.
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0.05%以上を含有することが好ましいが、含有量が多すぎると経済的に不利なだけでなく、溶接熱影響部の靱性が劣化するため、Niを添加する場合は0.50%を上限とする。 Ni: 0.50% or less Ni is an element effective for improving toughness and increasing strength. To obtain this effect, it is preferable to contain 0.05% or more, but if the content is too large, it is economical. This is not only disadvantageous, but also the toughness of the weld heat affected zone deteriorates. Therefore, when Ni is added, the upper limit is 0.50%.
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が、含有量が多すぎると溶接性が劣化するため、Crを添加する場合は0.50%を上限とする。 Cr: 0.50% or less Cr, like Mn, is an element effective for obtaining sufficient strength even at low C. To obtain this effect, it is preferable to contain 0.05% or more. If the amount is too large, weldability deteriorates, so when Cr is added, the upper limit is 0.50%.
Mo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が、含有量が多すぎると溶接性が劣化するため、Moを添加する場合は0.50%を上限とする。 Mo: 0.50% or less Mo is an element effective in improving toughness and increasing strength. To obtain this effect, it is preferable to contain 0.05% or more, but if the content is too large, welding is performed. When the Mo is added, the upper limit is 0.50%.
Nb,VおよびTiはいずれも、鋼板の強度および靭性を高めるために任意に添加することができる元素である。各元素とも、含有量が0.005%未満ではその添加効果に乏しく、一方0.1%を超えると溶接部の靭性が劣化するので、添加する場合はいずれも0.005~0.1%の範囲とするのが好ましい。 One or more selected from Nb: 0.005 to 0.1%, V: 0.005 to 0.1% and Ti: 0.005 to 0.1% Any of Nb, V and Ti Is an element that can be optionally added to increase the strength and toughness of the steel sheet. When the content of each element is less than 0.005%, the effect of addition is poor. On the other hand, when the content exceeds 0.1%, the toughness of the welded portion deteriorates. It is preferable to be in the range.
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。 This disclosure discloses a technique for improving the SSCC resistance of a high-strength steel pipe using a high-strength steel plate for sour line pipes. Needless to say, the sour-proof performance is not limited to HIC resistance. Since it is necessary to satisfy simultaneously, CP value calculated | required by the following (1) formula shall be 1.00 or less. Note that 0 may be substituted for elements not added.
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)
However, [% X] indicates the content (mass%) of element X in steel.
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。引張強さが520MPa以上の高強度化を図るために、鋼組織は、ベイナイト組織とする必要がある。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。ここで、ベイナイト組織は、変態強化に寄与する加速冷却時あるいは加速冷却後に変態するベイニティックフェライトまたはグラニュラーフェライトと称される組織を含むものとする。ベイナイト組織中に、フェライトやマルテンサイト、パーライト、島状マルテンサイト、残留オーステナイトなどの異種組織が混在すると、強度の低下や靭性の劣化、表層硬さの上昇などが生じるため、ベイナイト相以外の組織分率は少ない程良い。ただし、ベイナイト相以外の組織の体積分率が十分に低い場合には、それらの影響が無視できるので、ある程度の量であれば許容される。具体的に、本開示では、ベイナイト以外の鋼組織(フェライト、マルテンサイト、パーライト、島状マルテンサイト、残留オーステナイト等)の合計が体積分率で5%未満であれば、大きな影響がないので許容されるものとする。 [Structure of steel sheet]
Next, the steel structure of the high-strength steel sheet for sour line pipes according to the present disclosure will be described. In order to increase the tensile strength of 520 MPa or more, the steel structure needs to be a bainite structure. In particular, in the surface layer portion, when a hard phase such as martensite or island martensite (MA) is generated, the surface layer hardness is increased, the hardness variation in the steel sheet is increased, and the material uniformity is inhibited. . In order to suppress the increase in surface hardness, the steel structure of the surface layer portion is a bainite structure. Here, the bainite structure includes a structure called bainitic ferrite or granular ferrite that transforms during or after accelerated cooling that contributes to transformation strengthening. When different types of 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. The smaller the fraction, the better. However, when the volume fraction of the structure other than the bainite phase is sufficiently low, the influence thereof can be ignored, so that a certain amount is acceptable. Specifically, in the present disclosure, if the sum of the steel structures other than bainite (ferrite, martensite, pearlite, island martensite, residual austenite, etc.) is less than 5% in volume fraction, there is no significant influence, so Shall be.
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の加熱したのち、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い、その後鋼板を誘導加熱により再加熱する。 [Production method]
Hereinafter, the manufacturing method and manufacturing conditions for manufacturing the high-strength steel sheet for sour-resistant pipes will be specifically described. In the manufacturing method of the present disclosure, after heating a steel slab having the above composition, it is hot-rolled into a steel plate, and then the steel plate is subjected to controlled cooling under a predetermined condition, and then the steel plate is re-induced by induction heating. Heat.
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で必要な強度が得られず、一方1300℃を超えると靭性が劣化するため、スラブ加熱温度は1000~1300℃とする。なお、この温度は加熱炉の炉内温度であり、スラブは中心部までこの温度に加熱されるものとする。 [Slab heating temperature]
Slab heating temperature: 1000-1300 ° C
If the slab heating temperature is less than 1000 ° C., the required strength cannot be obtained due to insufficient solid solution of the carbide. On the other hand, if the slab heating temperature exceeds 1300 ° C., the toughness deteriorates, so the slab heating temperature is set to 1000 to 1300 ° C. This temperature is the furnace temperature of the heating furnace, and the slab is heated to this temperature up to the center.
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。また、高い母材靱性を得るためにはオーステナイト未再結晶温度域に相当する950℃以下の温度域での圧下率を60%以上とすることが望ましい。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。 [Rolling end temperature]
In the hot rolling process, in order to obtain a high base metal toughness, the lower the rolling end temperature, the better. However, on the other hand, the rolling efficiency decreases, so 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 strength and HIC resistance, it is preferable that the rolling end temperature is not less than the Ar 3 transformation point at the steel sheet surface temperature. Here, the Ar 3 transformation point means the ferrite transformation start temperature during cooling, and can be obtained from the steel components by the following formula, for example. In order to obtain high base metal toughness, it is desirable that the rolling reduction in a temperature range of 950 ° C. or lower corresponding to the austenite non-recrystallization temperature range be 60% or more. In addition, the surface temperature of a steel plate 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]
However, [% X] indicates the content (mass%) of element X in steel.
冷却開始時の鋼板表面温度T1:(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り、特にAr3変態点からの温度降下量が10℃を超えると体積分率で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性が劣化するため、冷却開始時の鋼板表面温度は(Ar3-10℃)以上とする。 [Cooling start temperature of control cooling]
Steel plate surface temperature T 1 at the start of cooling: (Ar 3 −10 ° C.) or more When the steel plate surface temperature at the start of cooling is low, the amount of ferrite produced before controlled cooling increases, and in particular, the temperature drop from the Ar 3 transformation point When the temperature exceeds 10 ° C., ferrite with a volume fraction exceeding 5% is generated, and the strength drop increases and the HIC resistance deteriorates. Therefore, the steel sheet surface temperature at the start of cooling is (Ar 3 −10 ° C.) or more. And
高強度化を図りつつ、鋼板内の硬さのばらつきを低減し、材質均一性を向上させるためには、表層(具体的には鋼板表面下0.5mmの深さ)での冷却速度を抑制しつつ、板厚中心の変態温度区間での冷却速度を確保する必要がある。 [Cooling rate of controlled cooling]
Suppressing the cooling rate on the surface layer (specifically, a depth of 0.5 mm below the surface of the steel sheet) in order to reduce the hardness variation in the steel sheet and improve the material uniformity while increasing the strength However, it is necessary to ensure the cooling rate in the transformation temperature section centered on the plate thickness.
鋼板表面下0.5mmにおける鋼板温度で750℃から550℃までの平均冷却速度が100℃/sを超えると、鋼板表面下0.5mmにおける転位密度7.0×1014(m-2)超えとなってしまう。その結果、鋼板表面下0.5mmのHV0.1が230を超え、造管後のコーティング過程を経たのち、表面下0.5mmでのHV0.1が260を超え、鋼管の耐SSCC性が劣化する。そのため、当該平均冷却速度は100℃/s以下とする。好ましくは80℃/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、10℃/s以上とすることが好ましい。 Average cooling rate from 750 ° C. to 550 ° C. at a steel plate temperature at 0.5 mm below the steel plate surface: 100 ° C./s or less Average cooling rate from 750 ° C. to 550 ° C. at a steel plate temperature at 0.5 mm below the steel plate surface is 100 ° C. / If it exceeds s, the dislocation density at 0.5 mm below the steel sheet surface exceeds 7.0 × 10 14 (m −2 ). As a result, HV0.1 of 0.5 mm below the steel sheet surface exceeds 230, and after passing through the coating process after pipe forming, HV0.1 at 0.5 mm below the surface exceeds 260, and the SSCC resistance of the steel pipe deteriorates. To do. Therefore, the said average cooling rate shall be 100 degrees C / s or less. Preferably it is 80 degrees C / s or less. The lower limit of the average cooling rate is not particularly limited. However, if the cooling rate is excessively small, ferrite and pearlite are generated and the strength becomes insufficient. Therefore, from the viewpoint of preventing this, it is preferably set to 10 ° C./s or more.
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性の劣化が生じたり、板厚方向の硬さのばらつきが大きくなったりする。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の観点からは、鋼板平均の冷却速度は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、低温変態生成物が過剰に生成しないように、80℃/s以下とすることが好ましい。 Average cooling rate from 750 ° C. to 550 ° C. at the average temperature of the steel plate: 15 ° C./s or more When the average cooling rate from 750 ° C. to 550 ° C. at the average temperature of the steel plate is less than 15 ° C./s, the bainite structure is not obtained and the strength Decrease and deterioration of HIC resistance occur, or the variation in hardness in the thickness direction increases. For this reason, the cooling rate at the steel plate average temperature is set to 15 ° C./s or more. From the viewpoint of variations in steel plate strength and hardness, the average cooling rate of the steel plate is preferably 20 ° C./s or more. The upper limit of the average cooling rate is not particularly limited, but is preferably set to 80 ° C./s or less so that the low temperature transformation product is not excessively generated.
鋼板平均温度で冷却停止温度T2:250~550℃
圧延終了後、制御冷却でベイナイト変態の温度域である250~550℃まで急冷することにより、ベイナイト相を生成させる。冷却停止温度が550℃を超えると、ベイナイト変態が不完全であり、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、マルテンサイトや島状マルテンサイト(MA)が生成し、特に板厚方向の硬さのばらつきが大きくなる。そこで、鋼板内の材質均一性の劣化を抑制するため、制御冷却の冷却停止温度は鋼板平均温度で250~550℃とする。 [Cooling stop temperature]
Steel sheet average temperature and cooling stop temperature T 2 : 250 to 550 ° C
After rolling, the bainite phase is generated by quenching to 250 to 550 ° C., which is the temperature range of bainite transformation, by controlled cooling. When the cooling stop temperature exceeds 550 ° C., the bainite transformation is incomplete and sufficient strength cannot be obtained. In addition, when the cooling stop temperature is less than 250 ° C., martensite and island martensite (MA) are generated, and in particular, the variation in hardness in the thickness direction becomes large. Therefore, in order to suppress deterioration of material uniformity in the steel plate, the cooling stop temperature of the controlled cooling is set to 250 to 550 ° C. as the steel plate average temperature.
誘導加熱温度T3:鋼板表面温度で550~750℃
本実施形態では、制御冷却後、制御冷却でベイナイト中に導入された高密度の転位を焼戻すことが重要である。これにより、鋼板表面下0.5mmにおける転位密度が7.0×1014(m-2)以下となり、優れた耐SSCC性が得られ、また、鋼板表面下0.5mmにおけるビッカース硬さの平均値と鋼板板厚中央におけるビッカース硬さの平均値との差ΔHVを25HV以下とすることができる。ここで、誘導加熱温度が550℃を下回ると、十分な焼き戻し効果が得られず、表層の転位密度を7.0×1014(m-2)以下とすることができても、ΔHVを25HV以下とすることはできない。また、誘導加熱温度が750℃を超えると、板厚中央も焼戻され、所定の強度を得られなくなる恐れがある。そこで、鋼板内の材質均一性の劣化を抑制しつつ板厚中央の強度を確保するため、オンライン誘導加熱の到達温度は鋼板表面温度で550~750℃とする。なお、本実施形態では、強度低下を抑えるために鋼板内部はなるべく焼き戻すことなく、表層部のみを焼き戻すことが肝要であり、そのため、加熱はオンライン誘導加熱装置を用いる。 [Induction heating conditions]
Induction heating temperature T 3 : 550 to 750 ° C. at the steel sheet surface temperature
In this embodiment, after the controlled cooling, it is important to temper the high-density dislocations introduced into the bainite by the controlled cooling. Thereby, the dislocation density at 0.5 mm below the steel sheet surface was 7.0 × 10 14 (m −2 ) or less, and excellent SSCC resistance was obtained, and the average of the Vickers hardness at 0.5 mm below the steel sheet surface was obtained. The difference ΔHV between the value and the average value of Vickers hardness at the center of the steel plate thickness can be 25 HV or less. Here, if the induction heating temperature is lower than 550 ° C., a sufficient tempering effect cannot be obtained, and even if the dislocation density of the surface layer can be 7.0 × 10 14 (m −2 ) or less, ΔHV is It cannot be less than 25HV. If the induction heating temperature exceeds 750 ° C., the center of the plate thickness is also tempered, and there is a possibility that a predetermined strength cannot be obtained. Therefore, in order to secure the strength at the center of the plate thickness while suppressing deterioration of material uniformity in the steel plate, the ultimate temperature of the on-line induction heating is set to 550 to 750 ° C. at the steel plate surface temperature. In the present embodiment, it is important that only the surface layer portion is tempered without tempering the inside of the steel sheet as much as possible in order to suppress a decrease in strength, and therefore, an online induction heating device is used for heating.
TP=(T3-T2)×T2/(T1-T2)2 ・・・(2)
TPは制御冷却の過冷度に対する焼き戻しの関係式であり、これが0.50以上を満たすことで、加速冷却で導入された表層部分の転位を十分に回復しつつ板厚中央での過度の焼き戻しをまねかないため、板厚方向における硬さのばらつきを顕著に抑制することが可能となる。具体的には、ΔHVを20以下とすることができる。 Regarding reheating conditions, it is preferable that TP defined by the following formula (2) satisfies 0.50 or more and 1.50 or less. More preferably, it is 0.60 or more and 1.00 or less.
TP = (T 3 −T 2 ) × T 2 / (T 1 −T 2 ) 2 (2)
TP is a relational expression of tempering with respect to the degree of supercooling of the controlled cooling, and when this satisfies 0.50 or more, the dislocation of the surface layer portion introduced by the accelerated cooling is sufficiently recovered and excessive in the center of the plate thickness. Since tempering is not imitated, it is possible to remarkably suppress variation in hardness in the thickness direction. Specifically, ΔHV can be set to 20 or less.
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。 [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, ERW steel pipes, spiral steel pipes, etc.) can be manufactured.
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。鋼板表面下0.5mmの位置での組織と、板厚中央での組織を、表2に示す。 [Identify organization]
The microstructure of the obtained steel sheet was observed with an optical microscope and a scanning electron microscope. Table 2 shows the structure at a position 0.5 mm below the surface of the steel sheet and the structure at the center of the plate thickness.
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、引張強度を測定した。結果を表2に示す。 [Measurement of tensile strength]
A tensile test was performed using a full-thickness test piece in a direction perpendicular to the rolling direction as a tensile test piece, and the tensile strength was measured. The results are shown in Table 2.
圧延方向に直角な断面について、JIS Z 2244に準拠して、鋼板表面下0.5mmの位置において20点のビッカース硬さ(HV0.1)を測定し、その平均値を求めた。また、板厚中央においても同様に20点のビッカース硬さ(HV0.1)を測定し、その平均値を求めた。そして、両者の差の絶対値ΔHVを求めた。ここで、通常用いられるHV10に代えてHV0.1で測定したのは、HV0.1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することが可能となるからである。 [Measurement of Vickers hardness]
With respect to the cross section perpendicular to the rolling direction, 20 points of Vickers hardness (HV0.1) were measured at a position 0.5 mm below the steel sheet surface in accordance with JIS Z 2244, and the average value was obtained. Similarly, 20 points of Vickers hardness (HV0.1) were measured at the center of the plate thickness, and the average value was obtained. And the absolute value (DELTA) HV of the difference of both was calculated | required. Here, instead of the normally used HV10, the measurement was performed with HV0.1, because the indentation is reduced by measuring with HV0.1, so the hardness information at a position closer to the surface and more sensitive to the microstructure This is because it is possible to perform accurate hardness information.
平均的な硬度を有する位置からX線回折用のサンプルを採取、サンプル表面を研磨してスケールを除去し、鋼板表面下0.5mmの位置においてX線回折測定を行った。転位密度はX線回折測定の半価幅βから求める歪みから換算する手法を用いた。通常のX線回折により得られる回折強度曲線では、波長の異なるKα1線とKα2線の2つが重なっているため、Rachingerの方法により分離する。歪みの抽出には、以下に示すWilliamsson-Hall法を用いる。半価幅の広がりは結晶子のサイズDとひずみεが影響し、両因子の和として次式で計算できる。β=β1+β2=(0.9λ/(D×cosθ))+2ε×tanθとなる。さらにこの式を変形し、βcosθ/λ=0.9λ/D+2ε×sinθ/λとなる。sinθ/λに対してβcosθ/λをプロットすることにより、直線の傾きからひずみεが算出される。なお、算出に用いる回折線は(110)、(211)、および(220)とする。ひずみεから転位密度の換算はρ=14.4ε2/b2を用いた。なお、θはX線回折のθ‐2θ法より算出されるピーク角度を意味し、λはX線回折で使用するX線の波長を意味する。bはFe(α)のバーガース・ベクトルで、本実施例においては、0.25nmとした。 [Dislocation density]
A sample for X-ray diffraction was collected from a position having an average hardness, the sample surface was polished to remove the scale, and X-ray diffraction measurement was performed at a position 0.5 mm below the steel sheet surface. The dislocation density was converted from the strain obtained from the half width β of the X-ray diffraction measurement. In the diffraction intensity curve obtained by normal X-ray diffraction, the Kα1 line and the Kα2 line having different wavelengths overlap each other, so that they are separated by the Rachinger method. The Williamsson-Hall method shown below is used for distortion extraction. The spread of the half width is affected by the size D of the crystallite and the strain ε, and can be calculated by the following equation as the sum of both factors. β = β1 + β2 = (0.9λ / (D × cos θ)) + 2ε × tan θ. Further, this equation is transformed to βcos θ / λ = 0.9λ / D + 2ε × sin θ / λ. By plotting β cos θ / λ against sin θ / λ, the strain ε is calculated from the slope of the straight line. The diffraction lines used for the calculation are (110), (211), and (220). For the conversion of the dislocation density from the strain ε, ρ = 14.4ε 2 / b 2 was used. Here, θ means the peak angle calculated by the θ-2θ method of X-ray diffraction, and λ means the wavelength of X-rays used in X-ray diffraction. b is a Burgers vector of Fe (α), and in this example, it was 0.25 nm.
耐SSCC性は、これら各鋼板の一部を用いて造管して評価した。造管は、鋼板の端部を開先加工し、Cプレス、Uプレス、Oプレスで鋼管形状に成形した後、内面および外面の突き合わせ部をサブマージアーク溶接でシーム溶接し、拡管工程を経て製造した。図1に示すように、得られた鋼管から切り出したクーポン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、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。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。720時間の浸漬後に、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。 [Evaluation of SSCC resistance]
SSCC resistance was evaluated by pipe forming using a part of each of these steel plates. Pipe making is performed after the end of the steel plate is grooved and formed into a steel pipe shape by C-press, U-press and O-press, then the butt part of the inner and outer surfaces is seam welded by submerged arc welding, and the tube is expanded. did. As shown in FIG. 1, after flattening a coupon cut out from the obtained steel pipe, 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 test surface, was left with a black skin to leave the outermost layer. The collected SSCC test piece was loaded with 90% of the actual yield strength (0.5% YS) of each steel pipe, and using NACE TM0177 Solution A solution, hydrogen sulfide partial pressure: 1 bar, EFC16 standard The four-point bending SSCC test was conducted. A case where no crack was observed after immersing for 720 hours was judged as good when the SSCC resistance was good, and a case where a crack occurred was judged as poor and was marked as x. The results are shown in Table 2.
耐HIC性は、NACE Standard TM-02-84に準じた浸漬時間96時間のHIC試験を行い、割れが認められない場合を耐HIC性良好と判断して○で、割れが発生した場合を×として評価した。結果を表2に示す。 [Evaluation of HIC resistance]
The HIC resistance was evaluated as “Good” when a HIC test was conducted with an immersion time of 96 hours in accordance with NACE Standard TM-02-84. As evaluated. The results are shown in Table 2.
According to the present invention, it is possible to supply a high-strength steel sheet for sour line pipes that is excellent in HIC resistance and SSCC resistance in a more severe corrosive environment and excellent in hardness uniformity in the thickness direction. . Therefore, a steel pipe (such as an electric resistance steel pipe, a spiral steel pipe, or a UOE steel pipe) manufactured by cold forming this steel sheet can be suitably used for transporting crude oil or natural gas containing hydrogen sulfide that requires sour resistance. .
Claims (8)
- 質量%で、C:0.02~0.08%、Si:0.01~0.50%、Mn:0.50~1.80%、P:0.001~0.015%、S:0.0002~0.0015%、Al:0.01~0.08%およびCa:0.0005~0.005%を含有し、以下の式(1)によって求められるCP値が1.00以下となり、残部がFeおよび不可避的不純物からなる成分組成を有し、
鋼板表面下0.5mmにおける鋼組織が、転位密度0.5×1014~7.0×1014(m-2)のベイナイト組織であり、
鋼板表面下0.5mmにおけるビッカース硬さの平均値と鋼板板厚中央におけるビッカース硬さの平均値との差ΔHVが25HV以下であり、
520MPa以上の引張強さを有する
ことを特徴とする耐サワーラインパイプ用高強度鋼板。
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。 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: It contains 0.0002 to 0.0015%, Al: 0.01 to 0.08%, and Ca: 0.0005 to 0.005%, and the CP value obtained by the following formula (1) is 1.00 or less And the remainder has a component composition consisting of Fe and inevitable impurities,
The steel structure at 0.5 mm below the steel sheet surface is a bainite structure having a dislocation density of 0.5 × 10 14 to 7.0 × 10 14 (m −2 ),
The difference ΔHV between the average value of Vickers hardness at 0.5 mm below the steel sheet surface and the average value of Vickers hardness at the center of the steel sheet thickness is 25 HV or less,
A high-strength steel sheet for sour line pipes, characterized by having a tensile strength of 520 MPa or more.
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)
However, [% X] indicates the content (mass%) of element X in steel. - 前記成分組成が、さらに、質量%で、Cu:0.50%以下、Ni:0.50%以下、Cr:0.50%以下およびMo:0.50%以下のうちから選んだ1種又は2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。 In addition, the component composition may be one by mass selected from Cu: 0.50% or less, Ni: 0.50% or less, Cr: 0.50% or less, and Mo: 0.50% or less. The high-strength steel sheet for sour-resistant pipes according to claim 1, containing two or more kinds.
- 前記成分組成が、さらに、質量%で、Nb:0.005~0.1%、V:0.005~0.1%およびTi:0.005~0.1%のうちから選んだ1種又は2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。 The component composition is further selected by mass% from Nb: 0.005 to 0.1%, V: 0.005 to 0.1%, and Ti: 0.005 to 0.1%. Or the high-strength steel plate for sour-resistant pipes of Claim 1 or 2 containing 2 or more types.
- 質量%で、C:0.02~0.08%、Si:0.01~0.50%、Mn:0.50~1.80%、P:0.001~0.015%、S:0.0002~0.0015%、Al:0.01~0.08%およびCa:0.0005~0.005%を含有し、以下の式(1)によって求められるCP値が1.00以下となり、残部がFeおよび不可避的不純物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T1:(Ar3-10℃)以上、
鋼板表面下0.5mmにおける鋼板温度で750℃から550℃までの平均冷却速度:100℃/s以下、
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
鋼板平均温度で冷却停止温度T2:250~550℃
の条件で制御冷却を行い、
その後、誘導加熱により、鋼板平均温度が前記冷却停止温度T2以上であって、かつ鋼板表面温度が550~750℃の加熱温度T3となるように前記鋼板を再加熱することを特徴とする耐サワーラインパイプ用高強度鋼板の製造方法。
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。 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: It contains 0.0002 to 0.0015%, Al: 0.01 to 0.08%, and Ca: 0.0005 to 0.005%, and the CP value obtained by the following formula (1) is 1.00 or less And the balance of the steel slab having the composition of Fe and inevitable impurities is heated to a temperature of 1000 to 1300 ° C. and then hot-rolled into a steel sheet,
After that,
Steel sheet surface temperature T 1 at the start of cooling: (Ar 3 −10 ° C.) or more,
Average cooling rate from 750 ° C. to 550 ° C. at a steel plate temperature at 0.5 mm below the steel plate surface: 100 ° C./s or less,
Average cooling rate from 750 ° C. to 550 ° C. at the steel plate average temperature: 15 ° C./s or more, and cooling stop temperature T 2 at the steel plate average temperature: 250 to 550 ° C.
Controlled cooling under the conditions of
Thereafter, the steel sheet is reheated by induction heating so that the average temperature of the steel sheet is equal to or higher than the cooling stop temperature T 2 and the steel sheet surface temperature is a heating temperature T 3 of 550 to 750 ° C. Manufacturing method of high strength steel plate for sour line pipes.
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)
However, [% X] indicates the content (mass%) of element X in steel. - 前記成分組成が、さらに、質量%で、Cu:0.50%以下、Ni:0.50%以下、Cr:0.50%以下およびMo:0.50%以下のうちから選んだ1種又は2種以上を含有する、請求項4に記載の耐サワーラインパイプ用高強度鋼板の製造方法。 In addition, the component composition may be one by mass selected from Cu: 0.50% or less, Ni: 0.50% or less, Cr: 0.50% or less, and Mo: 0.50% or less. The manufacturing method of the high strength steel plate for sour-resistant pipes of Claim 4 containing 2 or more types.
- 前記成分組成が、さらに、質量%で、Nb:0.005~0.1%、V:0.005~0.1%およびTi:0.005~0.1%のうちから選んだ1種又は2種以上を含有する、請求項4または5に記載の耐サワーラインパイプ用高強度鋼板の製造方法。 The component composition is further selected by mass% from Nb: 0.005 to 0.1%, V: 0.005 to 0.1%, and Ti: 0.005 to 0.1%. Or the manufacturing method of the high strength steel plate for sour-proof pipes of Claim 4 or 5 containing 2 or more types.
- 前記再加熱は、以下の式(2)で定義されるTPが0.50以上となる条件を満たすように行う、請求項4~6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の製造方法。
TP=(T3-T2)×T2/(T1-T2)2 ・・・(2) The high strength for a sour line pipe according to any one of claims 4 to 6, wherein the reheating is performed so as to satisfy a condition that TP defined by the following formula (2) is 0.50 or more. A method of manufacturing a steel sheet.
TP = (T 3 −T 2 ) × T 2 / (T 1 −T 2 ) 2 (2) - 請求項1~3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。
A high-strength steel pipe using the high-strength steel sheet for sour-resistant pipes according to any one of claims 1 to 3.
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JP2019510032A JP6844691B2 (en) | 2017-03-30 | 2018-03-28 | High-strength steel sheets for sour-resistant pipes and their manufacturing methods, and high-strength steel pipes using high-strength steel sheets for sour-resistant pipes |
BR112019020236-6A BR112019020236B1 (en) | 2017-03-30 | 2018-03-28 | HIGH STRENGTH STEEL SHEET FOR ACIDITY RESISTANT LINE TUBE, METHOD FOR MANUFACTURING THE SAME, AND HIGH STRENGTH STEEL TUBE |
KR1020197030351A KR20190129097A (en) | 2017-03-30 | 2018-03-28 | High strength steel sheet for internal sour line pipe, manufacturing method thereof and high strength steel pipe using high strength steel sheet for internal sour line pipe |
CN201880022412.1A CN110475894B (en) | 2017-03-30 | 2018-03-28 | High-strength steel sheet for acid-resistant line pipe, method for producing same, and high-strength steel pipe using high-strength steel sheet for acid-resistant line pipe |
EP18774336.4A EP3604592B1 (en) | 2017-03-30 | 2018-03-28 | High strength steel plate for sour-resistant line pipe, method for manufacturing same, and high strength steel pipe using high strength steel plate for sour-resistant line pipe |
KR1020217029888A KR20210118960A (en) | 2017-03-30 | 2018-03-28 | High strength steel plate for sour-resistant line pipe, method for manufacturing same, and high strength steel pipe using high strength steel plate for sour-resistant line pipe |
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Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0957327A (en) | 1995-08-22 | 1997-03-04 | Sumitomo Metal Ind Ltd | Scale removal method of steel plate |
JP2002327212A (en) | 2001-02-28 | 2002-11-15 | Nkk Corp | Method for manufacturing sour resistant steel sheet for line pipe |
JP2005060820A (en) * | 2003-07-31 | 2005-03-10 | Jfe Steel Kk | High strength steel sheet for line pipe excellent in anti-hic (hydrogen induced cracking) characteristic and its manufacturing method |
JP3711896B2 (en) | 2001-06-26 | 2005-11-02 | Jfeスチール株式会社 | Manufacturing method of steel sheets for high-strength line pipes |
JP3796133B2 (en) | 2000-04-18 | 2006-07-12 | 新日本製鐵株式会社 | Thick steel plate cooling method and apparatus |
JP3951429B2 (en) | 1998-03-30 | 2007-08-01 | Jfeスチール株式会社 | Manufacturing method of high strength steel sheet with small material difference in thickness direction |
JP3951428B2 (en) | 1998-03-30 | 2007-08-01 | Jfeスチール株式会社 | Manufacturing method of high strength steel sheet with small material difference in thickness direction |
JP2008056962A (en) * | 2006-08-30 | 2008-03-13 | Jfe Steel Kk | Steel sheet for high strength line pipe which is excellent in resistance to crack induced by hydrogen and has small reduction in yield stress due to bauschinger effect, and manufacturing method therefor |
JP2013139630A (en) * | 2011-12-09 | 2013-07-18 | Jfe Steel Corp | High strength steel sheet for sour-resistant line pipe excellent in material uniformity in the steel sheet and method for producing the same |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4317499B2 (en) * | 2003-10-03 | 2009-08-19 | 新日本製鐵株式会社 | High tensile strength steel sheet having a low acoustic anisotropy and excellent weldability and having a tensile strength of 570 MPa or higher, and a method for producing the same |
JP5223511B2 (en) * | 2007-07-31 | 2013-06-26 | Jfeスチール株式会社 | Steel sheet for high strength sour line pipe, method for producing the same and steel pipe |
JP5672916B2 (en) * | 2010-09-30 | 2015-02-18 | Jfeスチール株式会社 | High-strength steel sheet for sour line pipes, method for producing the same, and high-strength steel pipe using high-strength steel sheets for sour line pipes |
JP5516784B2 (en) * | 2012-03-29 | 2014-06-11 | Jfeスチール株式会社 | Low yield ratio high strength steel sheet, method for producing the same, and high strength welded steel pipe using the same |
WO2014115549A1 (en) * | 2013-01-24 | 2014-07-31 | Jfeスチール株式会社 | Hot-rolled steel plate for high-strength line pipe |
JP5950045B2 (en) * | 2013-12-12 | 2016-07-13 | Jfeスチール株式会社 | Steel sheet and manufacturing method thereof |
WO2017018108A1 (en) * | 2015-07-27 | 2017-02-02 | 新日鐵住金株式会社 | Steel pipe for line pipe and method for manufacturing same |
-
2018
- 2018-03-28 WO PCT/JP2018/012956 patent/WO2018181564A1/en unknown
- 2018-03-28 JP JP2019510032A patent/JP6844691B2/en active Active
- 2018-03-28 CN CN201880022412.1A patent/CN110475894B/en active Active
- 2018-03-28 KR KR1020217029888A patent/KR20210118960A/en not_active Application Discontinuation
- 2018-03-28 KR KR1020197030351A patent/KR20190129097A/en active Application Filing
- 2018-03-28 EP EP18774336.4A patent/EP3604592B1/en active Active
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0957327A (en) | 1995-08-22 | 1997-03-04 | Sumitomo Metal Ind Ltd | Scale removal method of steel plate |
JP3951429B2 (en) | 1998-03-30 | 2007-08-01 | Jfeスチール株式会社 | Manufacturing method of high strength steel sheet with small material difference in thickness direction |
JP3951428B2 (en) | 1998-03-30 | 2007-08-01 | Jfeスチール株式会社 | Manufacturing method of high strength steel sheet with small material difference in thickness direction |
JP3796133B2 (en) | 2000-04-18 | 2006-07-12 | 新日本製鐵株式会社 | Thick steel plate cooling method and apparatus |
JP2002327212A (en) | 2001-02-28 | 2002-11-15 | Nkk Corp | Method for manufacturing sour resistant steel sheet for line pipe |
JP3711896B2 (en) | 2001-06-26 | 2005-11-02 | Jfeスチール株式会社 | Manufacturing method of steel sheets for high-strength line pipes |
JP2005060820A (en) * | 2003-07-31 | 2005-03-10 | Jfe Steel Kk | High strength steel sheet for line pipe excellent in anti-hic (hydrogen induced cracking) characteristic and its manufacturing method |
JP2008056962A (en) * | 2006-08-30 | 2008-03-13 | Jfe Steel Kk | Steel sheet for high strength line pipe which is excellent in resistance to crack induced by hydrogen and has small reduction in yield stress due to bauschinger effect, and manufacturing method therefor |
JP2013139630A (en) * | 2011-12-09 | 2013-07-18 | Jfe Steel Corp | High strength steel sheet for sour-resistant line pipe excellent in material uniformity in the steel sheet and method for producing the same |
Cited By (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPWO2020067210A1 (en) * | 2018-09-28 | 2021-02-15 | Jfeスチール株式会社 | High-strength steel sheet for sour-resistant pipe and its manufacturing method, and high-strength steel pipe using high-strength steel sheet for sour-resistant pipe |
WO2020067210A1 (en) * | 2018-09-28 | 2020-04-02 | Jfeスチール株式会社 | High-strength steel sheet for sour-resistant line pipe, method for producing same, and high-strength steel pipe using high-strength steel sheet for sour-resistant line pipe |
WO2020067209A1 (en) * | 2018-09-28 | 2020-04-02 | Jfeスチール株式会社 | High-strength steel sheet for sour-resistant line pipe, method for producing same, and high-strength steel pipe using high-strength steel sheet for sour-resistant line pipe |
JPWO2020067209A1 (en) * | 2018-09-28 | 2021-02-15 | Jfeスチール株式会社 | High-strength steel sheet for sour-resistant pipe and its manufacturing method, and high-strength steel pipe using high-strength steel sheet for sour-resistant pipe |
EP3872219A4 (en) * | 2018-10-26 | 2021-12-15 | Posco | High-strength steel having excellent resistance to sulfide stress cracking, and method for manufacturing same |
JP2022505840A (en) * | 2018-10-26 | 2022-01-14 | ポスコ | High-strength steel with excellent sulfide stress corrosion cracking resistance and its manufacturing method |
JP7344962B2 (en) | 2018-10-26 | 2023-09-14 | ポスコ カンパニー リミテッド | High-strength steel material with excellent sulfide stress corrosion cracking resistance and method for producing the same |
JPWO2021020220A1 (en) * | 2019-07-31 | 2021-02-04 | ||
WO2021020220A1 (en) * | 2019-07-31 | 2021-02-04 | Jfeスチール株式会社 | High-strength steel sheet for sour resistant line pipe, manufacturing method thereof, and high-strength steel pipe made using high-strength steel sheet for sour resistant line pipe |
CN114174547A (en) * | 2019-07-31 | 2022-03-11 | 杰富意钢铁株式会社 | High-strength steel sheet for acid-resistant line pipe, method for producing same, and high-strength steel pipe using high-strength steel sheet for acid-resistant line pipe |
EP4006180A4 (en) * | 2019-07-31 | 2022-10-12 | JFE Steel Corporation | High-strength steel sheet for sour resistant line pipe, manufacturing method thereof, and high-strength steel pipe made using high-strength steel sheet for sour resistant line pipe |
RU2788419C1 (en) * | 2019-07-31 | 2023-01-19 | ДжФЕ СТИЛ КОРПОРЕЙШН | High-strength steel sheet for hydrogen sulfide-resistant main pipe, the method for its manufacture and high-strength steel pipe obtained using high-strength steel sheet for hydrogen sulfide-resistant main pipe |
JP7272442B2 (en) | 2019-07-31 | 2023-05-12 | Jfeスチール株式会社 | High-strength steel plate for sour-resistant linepipe, manufacturing method thereof, and high-strength steel pipe using high-strength steel plate for sour-resistant linepipe |
WO2021161366A1 (en) * | 2020-02-10 | 2021-08-19 | 日本製鉄株式会社 | Line pipe-use electric resistance welded steel pipe |
JPWO2021161366A1 (en) * | 2020-02-10 | 2021-08-19 | ||
JP7226595B2 (en) | 2020-02-10 | 2023-02-21 | 日本製鉄株式会社 | Electric resistance welded steel pipes for line pipes |
WO2023162571A1 (en) * | 2022-02-24 | 2023-08-31 | Jfeスチール株式会社 | Steel plate and method for manufacturing same |
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