WO2009148193A1 - Tôle d’acier à excellente résistance à l’acide et conduit d’acier pour tubes de canalisation - Google Patents

Tôle d’acier à excellente résistance à l’acide et conduit d’acier pour tubes de canalisation Download PDF

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Publication number
WO2009148193A1
WO2009148193A1 PCT/JP2009/060721 JP2009060721W WO2009148193A1 WO 2009148193 A1 WO2009148193 A1 WO 2009148193A1 JP 2009060721 W JP2009060721 W JP 2009060721W WO 2009148193 A1 WO2009148193 A1 WO 2009148193A1
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steel
sour resistance
amount
toughness
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PCT/JP2009/060721
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English (en)
Japanese (ja)
Inventor
澤村充
村木太郎
原卓也
朝日均
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新日本製鐵株式会社
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Priority to BRPI0915520 priority Critical patent/BRPI0915520B1/pt
Priority to CN200980120913.4A priority patent/CN102057070B/zh
Priority to JP2010515956A priority patent/JP4719313B2/ja
Publication of WO2009148193A1 publication Critical patent/WO2009148193A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the present invention is a high-strength steel plate that is resistant to hydrogen-induced cracking in an environment containing hydrogen sulfide (H 2 S), that is, excellent in sour resistance, and is used mainly for transportation of oil and natural gas. It relates to steel pipes for strength line pipes. Background art
  • the sour resistance refers to hydrogen-induced crack resistance (HIC resistance) and stress crack resistance (SSCC resistance) in a corrosive environment containing hydrogen sulfide.
  • HIC resistance hydrogen-induced crack resistance
  • SSCC resistance stress crack resistance
  • steel sheets are being strengthened from the perspective of improving transportation efficiency and reducing costs by reducing the thickness, and steel sheets are required to have high toughness in consideration of use in cold regions. Has been.
  • Patent Documents 1 and 2 have proposed a method for producing a high-strength steel sheet with improved low-temperature toughness and sour resistance.
  • reducing the content of C and A 1 and adding Ti embrittlement due to the hard phase is suppressed, and intragranular transformation is promoted to suppress toughness reduction.
  • the addition of a controls the morphology of M n S and improves sour resistance.
  • Patent Documents 3 and 4 propose steel sheets in which the elongation of M n S is suppressed by controlling the Ca content, the O content, and the S content.
  • sulfide inclusions such as M n S
  • steel sheets and steel pipes that suppress the coarsening of N b _ T i _C— N inclusions that are the origin of HIC are, for example, patents Prior art document proposed in Document 5
  • Patent Document 1 Japanese Patent Application Laid-Open No. 0 6-2 9 3 9 1 8
  • Patent Document 2 Japanese Patent Application Laid-Open No. 0 7 — 2 3 3 4 1 5
  • Patent Document 3 Japanese Patent Application Laid-Open No. 0-7 — 2 4 2 9 4 4
  • Patent Document 4 Japanese Patent Laid-Open No. 2 0 0 0-1 0 9 9 4 7
  • Patent Document Japanese Patent Laid-Open No. 2 0 0 6 — 6 3 3 5 1 Patent Summary of the Invention
  • the present invention has been made in view of such a situation, and aims to propose a steel plate excellent in sour resistance and a steel pipe for a line pipe.
  • the present inventors conducted an investigation to clarify the cause of the occurrence of HIC in a steel sheet with reduced S content and addition of Ca. As a result, the amount of S is reduced to 8 ppm or less, and the steel sheet with added Ca Regardless, we found that the starting point of HIC is MnS stretched over 50 m. Therefore, the present inventors further examined this cause and concluded that deoxidation was inappropriate, so that Ca was an oxide and MnS was coarsened. It was.
  • the present invention has been made based on such knowledge, and the gist thereof is as follows.
  • N b 0 • 0 1% or more, 0 • 0 4 7 or less
  • the balance consists of Fe and impurities, and the content [mass%] of A 1 and S i is A 1 ⁇ 0. 0 0 5% and 0.25% ⁇ S 1,
  • the Nb content is 0.01 to 0.02% by mass%, and the heat resistance according to any one of (1) to (4) above Excellent steel plate.
  • the amount of Ca is from 0.020 to 0.040% in terms of mass%, according to any one of the above (1) to (5), Steel sheet with excellent heat resistance.
  • V 0.10% or less
  • the steel sheet having excellent sour resistance according to any one of the above (1) to (8), characterized by comprising:
  • R E M 0.0 5% or less
  • the steel plate having excellent sour resistance according to any one of the above (1) to (10), characterized by containing one or more of the above.
  • the amount of S is reduced, the amount of O (oxygen) is reduced by the addition of an appropriate deoxidizing agent, and the addition of an appropriate amount of Ca suppresses the stretching of M n S.
  • the present invention it is possible to reliably prevent the occurrence of cracks due to the HIC of steel plates and steel pipes.
  • a 1 amount is low By reducing it, it becomes possible to improve the toughness of HAZ. Therefore, according to the present invention, it becomes possible to provide a steel plate and a steel pipe for line pipe excellent in sour resistance and further HA Z toughness, and the present invention has an extremely significant industrial contribution. . Brief Description of Drawings
  • FIG. 1 is a diagram showing an example of M n S stretched in the rolling direction.
  • Figure 2 is a diagram showing the relationship between the maximum length of M n S in steel sheets and 3 x 3 and ⁇ 3 1.
  • FIG. 3 is a view showing ranges of the Si amount and the A 1 amount of the steel sheet of the present invention.
  • HIC generated in the steel sheet with 0.005% Ca added and the amount of S being 0.000% is M n S extending in the rolling direction existing in the center segregation part. Note that% means mass%, and the same applies hereinafter.
  • the length of the stretched M n S exceeds 50 m.
  • This steel plate has 0.039% C, 0.24% Si, 1.20% Mn, and 0.00 as the main components other than S and Ca. 2 Contains 1% of ⁇ (oxygen), and further contains 0.01% or less of A1 and about 0.01% of Nb and Ti.
  • this result means that the fixation of S by Ca becomes insufficient when the oxygen amount exceeds 0.0 0 20%. Therefore, prolapse It is considered that the acid should be strengthened. Addition of A 1 is effective for strengthening deoxidation. On the other hand, when A 1 is added, there is a concern that the low-temperature toughness will decrease due to the increase in inclusions and the suppression of intragranular transformation. With the increase in the amount of A 1, MA is generated especially in HAZ, and it is thought that the low temperature toughness decreases due to this.
  • the present inventors tried to enhance deoxidation by increasing the amount of Si added in order to achieve both sour resistance and low temperature toughness.
  • S 1 is an element that reduces toughness
  • the upper limit of the amount of Si added was also examined.
  • a sample was taken from the location corresponding to the center segregation part of the steel sheet (12 parts in the thickness direction), and M n S was observed with a scanning electron microscope (S E M).
  • S E M scanning electron microscope
  • the lengths of longitudinally extending M n S and spherical M n S present in the field of view in the range of 50 mm square were measured. The measurement was performed at 15 locations on each steel plate, and the maximum measured M n S length was taken as the maximum M n S length of the steel plate.
  • FIG. 2 shows that when S / C a> 0.33, the elongation of M n S cannot be suppressed even if OZ S i is decreased.
  • S / C a ⁇ 0.33 ⁇ S i decreases and the elongation of M n S is remarkably suppressed, and when OS i becomes less than 0.005, M n It can be seen that the maximum length is suppressed to 20; m or less.
  • the resistance to corrosion is correlated with the maximum length of M n,
  • N b 0.0 1% or more, but less than 0.0 4%
  • C a 0.0 0 1 0
  • sour resistance we investigated the material properties of each sample in the TM 0 1 7 7 – 90 Method A environment specified by NA C E and measured the crack occurrence area ratio (C A R).
  • HA Z toughness was evaluated by taking a sample from a steel plate, performing a heat treatment (reproducible thermal cycle test) to simulate the thermal history of HA Z, and conducting a Charpy impact test. The reproducible thermal cycle test was conducted under the condition that induction heating was performed at 1400 and the cooling time from 800 to 50:00 was 3 8 s. The Charpy impact test was performed in accordance with JI S Z 2 2 4 2.
  • a 1 amount is not more than 0.0 0 5%
  • S i amount is more than 0.4 0%, 0.5 0% or less
  • a 1 amount is more than 0.0 0 5%, 0.0
  • the sour resistance is very good, but HA Z toughness is slightly reduced. I understood it.
  • the upper limit of the Si amount is preferably 0.40% or less.
  • the HA Z toughness of region 2 in Fig. 3 was found to be superior to that of region 4, which is inferior to region 1.
  • the amount of Si is 0.1% or more and less than 0 25%, and the amount of A 1 is 0.0 0.
  • the Si amount is 0.1% or more and less than 0.25%
  • the A1 amount is more than 0.050% and less than 0.02%
  • the amount of A1 per mass% This means that the deoxidation capacity is about 10 times that of S i.
  • the amount of A 1 is less than 0.0 0 50%, the amount of Si is less than 0.25%, and the amount of A 1 is more than 0.0 0 50% and less than 0.0 2 0 0% , S i amount is 0.1 0% or more and less than 0.2 5%, A 1 + 0. IS i ⁇ 0. 0 3%
  • S i is the most important element in the present invention, and is used as a deoxidizing agent.
  • H A Z toughness may be impaired.
  • the upper limit is made 0.5% or less.
  • the upper limit of the Si content is preferably set to 0.40% or less.
  • a 1 is a deoxidizing element, and is an effective element for suppressing the formation of Ca oxide and fixing S as C a S. If A 1 is added excessively, the low temperature toughness, particularly the HA Z toughness, is impaired by the formation of inclusions, so the content is limited to 0.040% or less. Since HA Z toughness is improved by reducing the amount of A 1, the upper limit is preferably made 0.020% or less. Furthermore, in order to suppress the formation of MA, and in particular to increase the low temperature toughness of HA Z, it is preferable to limit the amount to less than 0.005%.
  • the amount of A 1 is decreased, Ca oxide may be generated and Ca S may not be generated sufficiently.
  • the amount of A 1 is 0.05% or less, it is necessary to add 1 to 0.25% or more. If the amount of A 1 is more than 0.0 0 5%,
  • C a is an extremely important element that suppresses the formation of M n S and improves sour resistance. Even if the amount of S is reduced, in order to suppress the formation of M n S, addition of 0.0% or more is required. From the viewpoint of H A Z toughness, when the amount of A 1 is reduced, it is preferable to add Ca in an amount of 0.000% or more. On the other hand, if Ca is added excessively, inclusions become coarse and the toughness decreases, so the upper limit is made 0.0%.
  • the upper limit of the allowable content is set to 0.0 0 8%.
  • O is an impurity forming a Ca oxide added for controlling the form of sulfide.
  • the upper limit of the allowable content is set to 0.0 0 20%.
  • the content is preferably reduced to 0.001% or less.
  • the present inventors have found that, when Si is added to enhance deoxidation, MnS stretching can be suppressed, and as a result, generation of HIC can be suppressed. Based on this knowledge, the maximum suppression effect of HIC In order to secure the limit, it is necessary to adjust the amount of Ca and S i to be added (mass%, the same shall apply hereinafter) in relation to the amount of S and O. Therefore, the present inventors adopted S ZC a and OZ S i as indices.
  • C a is fixed as C a S and suppresses the generation of M n S. Therefore, it is 0.0 0 1 0% or more, and when the amount of A 1 is reduced, 0.0 0 Add 20% or more, but set the appropriate amount of Ca to be added for S fixation by S ZC a.
  • force S / C a> 0.3 3 is defined as S ZC a ⁇ 0.3 3
  • the amount of Ca is insufficient, and fixing S as C a S is insufficient. Become.
  • S i is added at least 0.1% or more, preferably 0.25% or more in order to sufficiently reduce the amount of O so that no Ca oxide is formed.
  • OZ S i ⁇ 0. 0 0 5 is specified.
  • ZS i> 0. 0 0 5 deoxidation by S i is insufficient, and the added Ca is an oxide. Does not contribute to the fixation of S.
  • OZ Si is more preferably less than 0.05.
  • C is an element that contributes to increasing the strength of the steel, and it is necessary to contain 0.0 1% or more. On the other hand, if C exceeds 0.08%, coarse carbides are formed especially in the central portion, and sour resistance is lowered. Therefore, the upper limit is set to 0.08%. In order to improve toughness, 0.07% or less is preferable.
  • M n is an element that improves hardenability, and is added at 1.0% or more. To improve strength and toughness, 1. 10% or more is preferred Yes. On the other hand, if M n exceeds 1.5%, center segregation becomes prominent and the sour resistance is impaired. Therefore, the upper limit is set to 1.5%. In order to suppress the formation of M n S and hard phase in the central segregation part and improve the sour resistance and toughness, it is preferable to set M n to 1.40% or less.
  • T i is an element that forms carbonitrides and contributes to refinement of the microstructure of steel, and also forms oxides that form the nuclei of intragranular transformation. Add 0.005% or more .
  • Ding 1 exceeds 0.030%, coarse carbonitrides are produced in the center and the sour resistance is lowered, so the upper limit is set to 0.030%.
  • it is 0.0 0.09 to 0.0 2 1%
  • Nb is an element that enhances hardenability and contributes to refinement of the steel structure by forming carbonitrides, and is added in an amount of 0.01% or more.
  • the upper limit is made less than 0.04%.
  • the upper limit is preferably made 0.02%.
  • a more preferable range of the Nb amount is 0.01 2 to 0.015%.
  • the upper limit is set to 0.0 15%. Preferably, it is not more than 0.0 0 1%.
  • N is an impurity, and when it is contained in excess, a nitride is formed in the central part and lowers the heat resistance. Therefore, the upper limit is preferably made 0.08% or less. In order to suppress the formation of nitrides and improve the HA Z toughness, the upper limit of the N content is preferably set to 0.05% or less.
  • V is a source of carbonitride that contributes to refinement of the steel structure. It is prime. In particular, in order to improve the strength and HA Z toughness, it is preferable to add 0.01% or more of V. However, if excessively added, coarse nitrides may be formed and HAZ toughness may be impaired, so the upper limit is preferably made 0.10% or less.
  • B is an element effective for improving hardenability.
  • the upper limit is preferably made 0.0% or less.
  • Mo, Cr, Ni and Cu which contribute to an improvement in intensity
  • Ni is also effective for improving toughness, so 0.15% or more is preferably added.
  • Mo, Cr, Ni, and Cu are added in excess of 0.5%, the weldability may be impaired. Therefore, the upper limit is set to 0.5%. .
  • both are 0.1 to 0.4%.
  • Mo, Cr, Ni, and Cu are elements that contribute to the improvement of corrosion resistance and are effective in improving sour resistance.
  • the upper limit is 0.3. It is preferable to be less than%. Further, with respect to Cr, the upper limit is preferably set to less than 0.3% from the viewpoint of the toughness of the weld heat affected zone and the field weldability.
  • Mg and REM which are effective for refinement of inclusions and control of the form of sulfide, may be added.
  • Mg is an element that forms fine oxides, suppresses the coarsening of the crystal grains in the heat affected zone, and improves toughness.
  • the upper limit of the Mg content is preferably 0.01% or less
  • the content of REM is The upper limit of the amount is preferably 0.05% or less. Since Mg and REM exhibit an effect even in a trace amount, a preferable lower limit of the content is 0.001% or more.
  • the steel is melted and forged by a conventional method, the obtained steel slab is heated, hot-rolled, and then accelerated cooled. Forging is preferably continuous forging from the viewpoint of productivity.
  • the heating temperature of the steel slab is preferably 1 100 or more so that MnS produced during forging is dissolved. On the other hand, if the heating temperature exceeds 1300, the crystal grain size may become coarse, so the heating temperature is preferably 1300 ° C or lower.
  • the finish rolling temperature of hot rolling is less than the Ar 3 transformation point, processed ferrite may be generated and toughness may be reduced.
  • the Ar 3 transformation point varies depending on the chemical composition and air cooling rate, use a sample taken from a steel slab or a sample that has almost the same component, and use a laboratory to simulate hot rolling and air cooling. It is preferable to obtain a three- point Ar by performing heat treatment and measuring transformation expansion.
  • the preferable range of the finish rolling temperature is 770 to 950. If the finish rolling temperature is 770 or more, the formation of C and Mn enriched layers in the center segregation part and the formation of a hardened phase of the metal structure are suppressed, and the resistance to hydrogen-induced cracking is improved. In order to refine the crystal grain size and improve the strength and toughness, the finish rolling temperature is preferably 950 or less.
  • the start temperature of accelerated cooling is less than (A r 3 transformation point 1 1 0 0)
  • a continuous pearlite hardening phase is generated at the center segregation part, which promotes the propagation of hydrogen-induced cracking.
  • the accelerated cooling may be water cooling.
  • the steel plate is formed into a tubular shape, and the seam is arc welded to form a steel pipe.
  • Table 1 Steels with the composition shown in Table 1 were melted and turned into billets by a continuous forging method. Table 1 also shows the composition ratio of S ZC a and OZ S i. The obtained steel slab was hot-rolled under the rolling conditions shown in Table 2 and subjected to accelerated cooling to produce a steel plate.
  • Airborne means no intentional addition.
  • Table 2 Take a specimen from the center of the thickness of the steel sheet and measure the length of M n S in the longitudinal direction existing in the field of view of a range of 5 O mm square at 30 points for each steel sheet using SEM. did.
  • the material property survey of each sample was conducted in the TM 0 1 7 7 — 90 Method A environment specified by NA CE, and the crack initiation area ratio (CAR ) Passed 0%. The results are shown in Table 3.
  • Steel Nos. 1 to 7 which are chemical components that satisfy all the scope of the present invention, have a CAR of less than 1%, and all show that excellent HIC resistance can be obtained.
  • Steel No. 1 0 3 has a high SC a
  • Steel No. 1 0 4 has a small amount of Ca
  • Steel No. 1 0 5 has an excessive amount of S.
  • I 0 5 stretched M n S and hydrogen-induced cracks starting from the stretched M n S were observed.
  • steel plates were piped in the UOE process, and the seam was submerged arc welded to produce steel pipes.
  • steel numbers 1 to 7 have a CAR of less than 1%
  • steel numbers 1001 to 105 have hydrogen-induced cracking starting from stretched MnS. It was. '
  • Table 4 Steels having the composition shown in Table 4 were melted and made into billets by the continuous forging method. Table 4 also shows the composition ratio of 3 3 and 0 3 i. The obtained steel slab was hot-rolled under the rolling conditions shown in Table 2 and subjected to accelerated cooling to produce a steel plate.
  • A1 More than 0.00053 ⁇ 4, less than 0.0200, Si: Only steel with 0.10 or more and less than 0.253 ⁇ 4 showed the calculated value of Al + 0.ISi.
  • HA Z toughness was evaluated by taking a specimen after a reproducible thermal cycle test and conducting a Charpy impact test in accordance with J I S Z 2 2 4 2.
  • the longitudinal direction of the test piece was the width direction of the steel sheet.
  • the regenerative heat cycle test was conducted under the condition of cooling from 8 0 00 to 5 0 00 in 38 seconds after induction heating to 1400.
  • the Charpy impact test was conducted while changing the test temperature, and the 50% fracture surface transition temperature was obtained. The results are shown in Table 5. Table 5
  • Steel Nos. 11 to 26 have a CAR of less than 1%, HA Z 50% fracture surface transition temperature is 0 and below, and sour resistance and HAZ toughness are good. is there.
  • Steel No. 20:! To 2 10 is a comparative example, and sour resistance or HA Z toughness is lowered.
  • Steel No. 2 0 1 has high OZ S i
  • Steel No. 2 0 2 has high S ZC a
  • Steel No. 2 0 3 has a large amount of S
  • HA Z toughness is good, but M n S is stretched The sour resistance is reduced.
  • Steel No. 2 0 4 has a large amount of O and good HA Z toughness, but has low sour resistance.
  • Steel No. 2 0 6 has low A 1 + 0. 1 Si, and Steel No. 2 0 7 has low A 1 and S i contents, so HA Z toughness is good, but sour resistance is reduced. ing.
  • Steel No. 20 07 has a large amount of Si, and steel No. 20 08 has a large amount of A 1, so the sour resistance is good, but the HAZ toughness is reduced.
  • Steel No. 20 9 is an example where the Nb content is high and the HAZ toughness is reduced.
  • Steel No. 2 1 0 has a small amount of Ca and has low sour resistance.
  • steel plates were piped in the UOE process, and the seam was submerged arc welded to produce steel pipes.
  • steel numbers 11 to 26 had good sour resistance and good toughness in the HA Z part.
  • steel numbers 2 0 1 to 2 1 0 were confirmed to have reduced sour resistance or HA Z toughness.

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Abstract

La présente concerne une tôle d’acier à excellente résistance à l’acide et conduit d’acier pour tubes de canalisation. La tôle d’acier et le conduit d’acier sont caractérisés en ce qu’ils contiennent en poids: 0,01 à 0,8% de C; 0,10 à 0,50% de Si; 1,00 à 1,50% de Mn; 0,005 à 0,030% de Ti; 0,01 mais n’excédant pas 0,04% de Nb; 0,0010 à 0,0040% de Ca; moins de 0,015 de P; moins de 0,0008% de S; moins de 0,0020 de O; moins de 0,040% d’Al; le reste étant Fe et des impuretés. L’invention est caractérisée en ce que la teneur (en pourcentage pondéral) d’Al et de Si satisfait les relations : Al > 0,005 et Al + 0,1Si > 0,03% et la teneur (en pourcentage pondéral) de S, O, Si, et Ca satisfait les relations : S/Ca < 0,33 et O/Si < 0,005.
PCT/JP2009/060721 2008-06-06 2009-06-05 Tôle d’acier à excellente résistance à l’acide et conduit d’acier pour tubes de canalisation WO2009148193A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
BRPI0915520 BRPI0915520B1 (pt) 2008-06-06 2009-06-05 chapa de aço com resistência à corrosão em meio sulfuroso
CN200980120913.4A CN102057070B (zh) 2008-06-06 2009-06-05 抗硫性优异的钢板和管线管用钢管
JP2010515956A JP4719313B2 (ja) 2008-06-06 2009-06-05 耐サワー性に優れた鋼板及びラインパイプ用鋼管

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JP2008-149708 2008-06-06
JP2008149708 2008-06-06

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JP2013124398A (ja) * 2011-12-15 2013-06-24 Jfe Steel Corp 高強度耐サワーラインパイプ用鋼板及びその素材
CN103499011A (zh) * 2013-09-24 2014-01-08 中国石油集团工程设计有限责任公司 一种抗硫厚板及其焊接工艺
JP2016125138A (ja) * 2014-12-26 2016-07-11 株式会社神戸製鋼所 耐水素誘起割れ性に優れた鋼板およびラインパイプ用鋼管
JP2016125137A (ja) * 2014-12-26 2016-07-11 株式会社神戸製鋼所 耐水素誘起割れ性に優れた鋼板およびラインパイプ用鋼管

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CN113106354A (zh) * 2021-03-31 2021-07-13 五矿营口中板有限责任公司 一种易焊接耐油气腐蚀造船结构钢及其制造方法

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