WO2024024236A1 - Acier faiblement allié résistant au craquage microbiologiquement assisté - Google Patents

Acier faiblement allié résistant au craquage microbiologiquement assisté Download PDF

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Publication number
WO2024024236A1
WO2024024236A1 PCT/JP2023/019060 JP2023019060W WO2024024236A1 WO 2024024236 A1 WO2024024236 A1 WO 2024024236A1 JP 2023019060 W JP2023019060 W JP 2023019060W WO 2024024236 A1 WO2024024236 A1 WO 2024024236A1
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corrosion
content
microbial
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PCT/JP2023/019060
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English (en)
Japanese (ja)
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至 寒澤
純二 嶋村
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Ｊｆｅスチール株式会社
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Priority to JP2023553947A priority Critical patent/JPWO2024024236A1/ja
Publication of WO2024024236A1 publication Critical patent/WO2024024236A1/fr

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    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a microbial stress corrosion cracking resistant steel material suitable for structural members such as automobile parts, power generation equipment parts, chemical plant parts, architectural parts, machine parts, ship parts, and oil field incidental equipment parts. .
  • Microbial corrosion is a highly localized corrosion phenomenon, and microbial corrosion that occurs in structures can become the starting point for through holes and stress corrosion cracking, which can lead to serious accidents.
  • MAC Computerobiologically Assisted Cracking
  • stress corrosion cracking assisted by microbial corrosion is one of the stress corrosion cracking phenomena that is a concern in real environments where microorganisms exist.
  • Common countermeasures against microbial corrosion include reducing the number of microorganisms present in the environment using disinfectants and physically removing microorganisms attached to materials (cleaning with brushes, etc.).
  • microbial corrosion there are limits to the reduction of microbial corrosion by these means. For example, it is difficult to physically clean the outer surface of a pipeline buried in soil, and it is also difficult to actively use disinfectants due to the impact on the soil environment. Therefore, there is increasing interest in approaches that increase the microbial corrosion resistance of materials. In line with this trend, attempts have been made in the field of steel materials to impart resistance to microbial corrosion.
  • a layer containing zinc is provided between a steel material and an epoxy resin coating, and the layer containing zinc is a layer consisting only of zinc, or a layer containing 85% by mass or more of zinc, and other configurations.
  • a method for preventing corrosion and paint peeling of a steel material has been reported, which is characterized by a layer made of an alloy containing any one of nickel, aluminum, magnesium, and iron as an element.
  • Patent Document 2 an outer layer consisting of a Cr(III)-Fe(III)-based hydroxide and an inner layer of a film mainly composed of a Cr(III)-based oxide and/or hydroxide are formed on the surface.
  • a stainless steel with excellent microbial corrosion resistance characterized by having a two-layer coating has been reported.
  • Patent Document 3 in mass %, Cu: 0.010% or more and less than 2.000%, Ni: 0.010% or more and 2.000% or less, Mo: 0.010% or more and 1.000% or less, By containing one or more selected from W: 0.010% to 1.000% and Sn: 0.010% to 0.500%, antibacterial properties and microbial corrosion resistance properties are enhanced. Steel materials have been proposed.
  • Non-Patent Document 1 reports that corrosion acceleration by SRB is based on the direct extraction of electrons from steel materials by SRB. That is, in the metabolic activity of SRB, SRB present on the surface of the steel material directly oxidizes Fe, thereby promoting dissolution of the steel material. S 2- ions produced as a result of this metabolic activity combine with Fe 2+ ions produced as a result of steel material corrosion, and a hardly soluble FeS film is formed on the steel surface. Since this FeS coating acts as a corrosion-resistant coating, it is generally believed that it contributes to reducing corrosion of steel materials.
  • the above conventional technology has the following problems.
  • Patent Document 1 The method for preventing corrosion of steel described in Patent Document 1 is considered to have sufficient antibacterial properties, but it requires painting and forming an alloy film, making it very expensive, so it requires particularly high corrosion resistance. This will result in excessive performance for applications other than those in severe applications. In other words, it is not practical to use it for parts to which low-alloy steel is originally applied due to cost considerations. Furthermore, if the surface is scratched due to impact, cuts, etc., the durability of the scratched portion cannot be expected, making it difficult to obtain long-term effects.
  • Patent Document 2 the technology described in Patent Document 2 is also considered to be effective as a measure to improve the microbial corrosion resistance of stainless steel materials, but it is not suitable for cost reasons for parts for which inexpensive low-alloy steel materials are expected to be applied. is difficult. Further, as in Patent Document 1, resistance to microbial corrosion cannot be ensured at locations where the surface is scratched and the coating structure effective in microbial corrosion resistance is lost.
  • microbial corrosion resistance is evaluated based on local corrosion in an actual seawater environment containing sulfate-reducing bacteria, which are corrosive bacteria. In real environments, microbial corrosion becomes apparent in areas where corrosive bacteria become locally active and the bacteria concentration is high. Not expected.
  • the technology described in Patent Document 3 is simply the result of evaluating local corrosion in a seawater corrosive environment, and is particularly uncertain as a technology for reducing stress corrosion cracking induced by microbial corrosion. .
  • stress corrosion cracking in the present invention refers to the MAC phenomenon in a broad sense, which includes not only a static stress environment but also a dynamically changing stress environment, that is, a stress environment equivalent to low cycle corrosion fatigue. say.
  • the inventors have made extensive studies to solve the above problems.
  • SRB stress corrosion cracking phenomenon induced by sulfate-reducing bacteria
  • Non-Patent Document 1 we obtained the following findings. That is, in a microbial corrosion environment where SRB exists, a film of FeS, which is a corrosion product, is formed on the surface of the steel material as a result of the metabolic reaction of SRB and the corrosion reaction of the steel material. Since this FeS film has conductivity, it has the property of promoting the cathode reaction, and on the other hand, since it acts as a physical protective film, it suppresses the anodic dissolution reaction.
  • SRB stress corrosion cracking phenomenon induced by sulfate-reducing bacteria
  • the microbial corrosion environment is essentially an environment with high local corrosivity. Furthermore, if this FeS coating is mechanically destroyed due to the presence of external stress, galvanic corrosion occurs, with the FeS coating fractured part as the anode site and the FeS coating remaining part as the cathode site, resulting in a significant local corrosion phenomenon.
  • This locally corroded area becomes an oxygen-deficient environment, which increases the activity of SRB, which is an anaerobic bacterium, and causes the direct oxidation (iron dissolution) reaction due to the metabolism of SRB to proceed at an accelerated pace.
  • the component composition is a microbial stress corrosion cracking resistant low alloy steel material further containing one or more of the following groups A to E in mass %.
  • Group A Ni: 0.01-4.00%, Group B; Cr: 0.01-4.00%, Sb: 0.01-0.50%, Sn: 0.01-0.50%, Mo: 0.01-2.00% and W: 0
  • Group D selected from Ti: 0.005-0.100%, Zr: 0.005-0.100%, Nb: 0.005-0.100% and V: 0.005-0.100%
  • the present invention when used for structural members such as automobile parts, power generation equipment parts, chemical plant parts, architectural parts, machine parts, ship parts, and oil field incidental equipment parts, compared to conventional ones, It is possible to obtain inexpensive low-alloy steel materials that are resistant to microbial stress corrosion cracking. Further, the present invention is extremely useful industrially.
  • % representing the content of each component element means “% by mass” unless otherwise specified.
  • C 0.30% or less C is an element necessary to ensure the strength of steel, and if the content exceeds 0.30%, workability and weldability will deteriorate significantly, so it is limited to 0.30% or less. Preferably it is 0.25% or less, more preferably 0.20% or less. Note that the lower limit is not particularly limited, but is preferably 0.02% or more.
  • Mn 0.10-3.00% Mn is added to improve strength and toughness, but if it is less than 0.10%, the effect is not sufficient, and if it exceeds 3.00%, weldability deteriorates, so the Mn content is 0.10%. 3.00% or less. Preferably it is 0.20% or more and 2.50% or less, more preferably 0.30% or more and 2.00% or less.
  • P 0.030% or less
  • the P content increases, toughness and weldability deteriorate, so the P content was suppressed to 0.030% or less.
  • it is 0.025% or less. Since it is difficult to reduce the content to less than 0.002% in industrial scale production, a content of 0.002% or more is permissible.
  • N 0.0100% or less Since N is a harmful element that reduces toughness, it is desirable to reduce it as much as possible. In particular, when the amount of N exceeds 0.0100%, the decrease in toughness becomes large. Therefore, the N content is set to 0.0100% or less. Preferably it is 0.0080% or less. More preferably, it is 0.0070% or less. Note that the lower limit is not particularly limited, but it is preferably 0.0005% or more, since excessive reduction in N content leads to an increase in cost.
  • Si 0.02 ⁇ 1.00% Si is a very important element from the viewpoint of improving microbial stress corrosion cracking resistance. That is, Si is eluted to the surface of the steel material as Si 2+ ions as the steel material corrodes in an environment where SRB exists. A reaction to form FeS occurs in a corrosive environment due to the reaction between S 2 ⁇ ions and Fe 2+ ions that occur along with the metabolic reaction of SRB. These liberated Si 2+ ions are incorporated into the crystal structure of FeS to form a local SiS structure within the macroscopic FeS structure. This Si-substituted FeS has a non-uniform crystal structure, so its conductivity is significantly reduced.
  • the Si content is 0.02% or more, preferably 0.03% or more, and more preferably 0.05% or more.
  • the formation reaction of this Si-substituted FeS is strongly influenced by the amount of S, O, and Al in the steel material.
  • the content is set to 1.00% or less, preferably 0.80% or less, and more preferably 0.70% or less.
  • S 0.0002-0.0100% 8 ⁇ Si(%)/S(%) ⁇ 1200
  • S in the steel material is eluted onto the surface of the steel material as it corrodes. If the eluted Si 2+ ions remain as they are, they do not have sufficient affinity with FeS, and therefore, the incorporation of Si into the FeS structure does not proceed sufficiently.
  • S eluted from the steel material quickly reacts with Si 2+ ions to form a core structure of SiS.
  • the SiS core structure has a high affinity with the FeS structure and promotes the incorporation of Si into the FeS structure.
  • the S content required to obtain this effect is 0.0002% or more. Preferably it is 0.0003% or more.
  • S is a harmful element that deteriorates the toughness and weldability of steel. In particular, when the S content exceeds 0.0100%, the deterioration of base metal toughness and weld zone toughness increases. Therefore, the S content is 0.0100% or less, preferably 0.008% or less, and more preferably 0.007% or less.
  • Al 0.003-0.500%
  • Al is an element added as a deoxidizer, and the Al content is 0.003% or more. However, when the Al content exceeds 0.500%, the toughness of the steel decreases. Therefore, the Al content is 0.003 to 0.500%, preferably 0.003 to 0.300%. Further, Al is an element that influences the expression of the effect of improving microbial stress corrosion cracking resistance due to Si. For this reason, it is necessary to appropriately manage the ratio between the amount of Al and the amount of O, as described below.
  • O 0.0005-0.0050% 3 ⁇ Al(%)/O(%)
  • O is an important element that must be controlled in order to obtain the effect of suppressing galvanic corrosion by Si. That is, like Si, O in the steel material is eluted onto the surface of the steel material as it corrodes. If this eluted O is present in excess, it combines with Si to form SiO 2 . As a result, the formation of SiS nuclei is inhibited, and the formation of Si-substituted FeS does not proceed. This SiO 2 formation becomes obvious when the O content exceeds 0.0050%, so the O content is set to 0.0050% or less. Preferably it is 0.0045% or less, more preferably 0.0040% or less.
  • the lower limit is not particularly limited in view of the characteristics of the steel material, but is 0.0005% or more because excessive reduction in the amount of O will lead to an increase in manufacturing costs in the steel manufacturing process.
  • it is 0.0006% or more, more preferably 0.0008% or more.
  • the content ratio of O (%) to Al (%) must be increased. Needs to be managed appropriately. That is, Al combines with O to quickly form Al 2 O 3 . The O liberated with the dissolution of the base material is quickly consumed by the Al liberated in this way, thereby suppressing the SiO 2 formation reaction and progressing the Si-substituted FeS formation reaction. The formation of Si-substituted FeS due to the rapid formation of Al 2 O 3 from Al and O becomes obvious when Al (%) / O (%) is 3 or more.
  • %) shall be 3 or more.
  • the upper limit is not particularly determined, but as mentioned above, increasing Al (%)/O (%) will reduce the amount of O excessively, which will reduce the manufacturing cost in the steelmaking process. Since it leads to an increase, it is preferable to set it to 150 or less.
  • Cu and Ag has a high resistance to resistance in the low alloy steel material of this embodiment. It is an essential element to obtain microbial stress corrosion cracking resistance.
  • Cu and Ag are liberated from the steel as Cu 2+ ions and Ag + ions, respectively, as the steel material elutes. These free ions are taken up by microorganisms on the surface of the steel material and strongly bind to -SH group-containing amino acids and proteins present in the enzyme systems of the microorganisms, thereby inhibiting the metabolic activities of the microorganisms.
  • the effect of suppressing localized corrosion as microbial stress corrosion cracking based on this microbial metabolic inhibition effect can be achieved by containing 0.02% or more of Cu, or by containing 0.01% or more of Ag, or by containing 0.01% or more of Cu. It can be obtained by containing 0.02% or more of Ag and 0.01% or more of Ag.
  • the Cu content is 0.02 to 3.00%. Preferably it is 0.05 to 2.00%, more preferably 0.10 to 1.50%. Further, the content of Ag is 0.01 to 0.50%. Preferably it is 0.01 to 0.30%, more preferably 0.02 to 0.20%.
  • the Ag content is less than 0 to 0.01%. Also, when the Ag content is 0.01 to 0.50%, the Cu content is 0 to less than 0.02%.
  • the basic components of this embodiment have been explained above.
  • the remainder other than the above components is Fe and inevitable impurities.
  • the Ni content is less than 0.01%
  • the Cr content is less than 0.01%
  • the Sb content is less than 0.01%
  • the Sn content is less than 0.01%
  • the Mo content is 0.01%.
  • W content is less than 0.01%
  • Ca content is less than 0.0001%
  • Mg content is less than 0.0001%
  • REM content is less than 0.001%
  • Ti content is 0.005%
  • a range in which the Zr content is less than 0.005%, the Nb content is less than 0.005%, the V content is less than 0.005%, and the B content is less than 0.0001% is treated as an unavoidable impurity.
  • the following elements may be contained as appropriate.
  • Ni 0.01-4.00% Ni can be added to improve the manufacturability of steel sheets. In order to obtain this effect, the Ni content is 0.01% or more. On the other hand, excessive Ni content causes deterioration in weldability and increase in manufacturing cost. Therefore, the Ni content is 4.00% or less. Preferably it is 3.00% or less, more preferably 2.00% or less. More preferably, it is 1.5% or less.
  • Cr 0.01 ⁇ 4.00%
  • Sb 0.01 ⁇ 0.50%
  • Sn 0.01 ⁇ 0.50%
  • Mo 0.01 ⁇ 2.00%
  • W 0.01 ⁇ 2.00% of one or more selected from among Cr, Sb, Sn, Mo, and W are elements that improve corrosion resistance in a wet environment where microbial corrosion occurs, especially in a seawater environment. Therefore, apart from microbial corrosion, one or more types can be contained for the purpose of improving seawater corrosion resistance. However, if the addition amount is large, it will cause deterioration of the toughness of the welded part and increase the manufacturing cost. 01 to 0.50%, Mo: 0.01 to 2.00%, and W: 0.01 to 2.00%.
  • Ca, Mg, and REM are One or more types selected from Ca: 0.0001 to 0.0100%, Mg: 0.0001 to 0.0200%, and REM: 0.001 to 0.200%
  • Ca, Mg, and REM are One or more types can be contained for the purpose of ensuring toughness. However, if the amount added is large, it will cause deterioration of the toughness of the welded part and increase manufacturing cost, so the Ca content should be 0.0001% or more and 0.0100% or less, and the Mg content should be 0.0001% or more and 0.01% or less. 0.0200% or less, and the REM content is 0.001% or more and 0.200% or less.
  • Ti 0.005 to 0.100%
  • Zr 0.005 to 0.100%
  • Nb 0.005 to 0.100%
  • V 0.005 to 0.100%
  • Ti, Zr, Nb, and V can be contained in order to ensure the desired strength. However, if too much of either is contained, the toughness and weldability will deteriorate, so the content should be 0.005% or more and 0.100% or less. Preferably it is 0.005% or more and 0.05% or less.
  • B 0.0001-0.0300%
  • B is an element that improves the hardenability of steel materials. Moreover, B can be contained for the purpose of ensuring the strength of the steel material. However, if it is contained in excess, the toughness will be significantly deteriorated. The strength improvement effect is poor when the B content is less than 0.0001%, and the deterioration of toughness becomes significant when it exceeds 0.0300%. Therefore, the B content is 0.0001% or more. 0300% or less.
  • Molten steel having the above-mentioned composition is melted in a known furnace such as a converter or an electric furnace, and is made into a steel material such as a slab or billet by a known method such as a continuous casting method or an ingot forming method.
  • a known furnace such as a converter or an electric furnace
  • a steel material such as a slab or billet
  • a known method such as a continuous casting method or an ingot forming method.
  • vacuum degassing refining or the like may be performed upon melting.
  • a known steel smelting method may be used to adjust the composition of the molten steel.
  • the heating temperature is preferably 1030°C or higher.
  • heating above 1350°C causes surface marks and increases scale loss and fuel consumption, so it is preferably 1350°C or lower. More preferably it is 1050 to 1300°C.
  • the temperature of the steel material is originally in the range of 1030 to 1350° C., it may be directly subjected to hot rolling without being heated.
  • reheating treatment, pickling, and cold rolling may be performed to obtain a cold rolled sheet having a predetermined thickness.
  • the finish rolling end temperature be 600°C or higher. If the finish rolling end temperature is less than 600° C., the rolling load increases due to an increase in deformation resistance, making it difficult to carry out rolling. Cooling after finish rolling in hot rolling is preferably performed by air cooling or accelerated cooling at a cooling rate of 150° C./s or less, but this does not apply when heat treatment is performed in a subsequent step.
  • test piece was taken from the above-mentioned hot-rolled steel sheet, and a corrosion fatigue test was performed on the test piece using a sulfate-reducing bacteria culture solution (SRB culture solution) to evaluate microbial stress corrosion cracking characteristics.
  • SRB culture solution a sulfate-reducing bacteria culture solution
  • vulgaris NBRC104121 was added to a screw cap test tube containing 5 mL of MB medium, and cultured at 37° C. for 4 days. Approximately 2.5 mL of the culture solution was then added to a sterile centrifuge tube containing fresh MB medium (1 L) in an anaerobic glove box.
  • a tensile test piece with a parallel portion of 6 mm ⁇ x 25 mm was taken so that the C direction (width direction) of the steel plate was the tensile direction of the test piece.
  • a tensile test was conducted at room temperature in accordance with the provisions of JIS Z 2241, and the yield strength (YS) of the steel plate was determined in order to calculate the stress to be applied in the corrosion fatigue test described below.
  • the steel plate was processed into a round bar of 130 mm x 6.35 mm ⁇ , and both ends were threaded. This round bar was machined to a diameter of 3.81 mm by 12.7 mm from the center to both ends to create a corrosion fatigue test piece with a parallel portion having a length of 25.4 mm.
  • This parallel portion corresponds to the C direction (sheet width direction) of the steel plate.
  • This corrosion fatigue test piece was subjected to ultrasonic degreasing in acetone for 5 minutes, and then attached to a corrosion fatigue tester.
  • NS4 aqueous solution containing 95% by mass of .181 g/L CaCl 2 .2H 2 O
  • an anaerobic gas (95 vol.% N 2 + 5 vol.
  • test pieces were taken out after the test, and the appearance was observed using a microscope with a 500x field of view to confirm the presence or absence of cracks.
  • test pieces in which cracks were confirmed the cross section was observed, the maximum crack length in the cross section was measured, and the crack propagation distance was calculated.
  • Microbial stress corrosion cracking resistance was evaluated based on the following criteria. For cracks with a length of less than 30 ⁇ m, crack propagation was slow and the risk of corrosion destruction was determined to be low.
  • the unit of volume "L" herein represents 10 ⁇ 3 m 3 .

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
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Abstract

L'invention concerne un acier faiblement allié résistant au craquage microbiologiquement assisté qui est pratique en termes de production. L'acier faiblement allié résistant au craquage microbiologiquement assisté comprend C : 0,30 % ou moins, Mn : 0,10-3,00 % ; P : 0,030 % ou moins, N : 0,0100 % ou moins, Si : 0,02 - 1,00 %, S : 0,0002-0,0100 %, Al : 0,003-0,500 %; O : 0,0005 - 0,0050 %, et comprend en outre un ou deux éléments choisis parmi Cu : 0,02-3,00 % et Ag : 0,01 à 0,50 %, le reste étant une composition de composants comprenant du Fe et des impuretés inévitables. Le rapport de teneur de Si sur S, Si (%)/S (%), est de 8 à 1200, et le rapport de teneur d'Al sur O, Al (%)/O (%), est d'au moins 3.
PCT/JP2023/019060 2022-07-29 2023-05-23 Acier faiblement allié résistant au craquage microbiologiquement assisté WO2024024236A1 (fr)

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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005179699A (ja) * 2003-12-16 2005-07-07 Nippon Steel Corp ステンレス鋼の電位貴化抑制方法
CN103741056A (zh) * 2014-01-26 2014-04-23 北京科技大学 一种耐南海海洋环境用耐蚀钢板及其生产工艺
JP2017190522A (ja) * 2016-04-11 2017-10-19 Ｊｆｅスチール株式会社 鋼材
WO2019035329A1 (fr) * 2017-08-15 2019-02-21 Ｊｆｅスチール株式会社 Tuyau sans soudure en acier inoxydable hautement résistant pour puits de pétrole, et procédé de fabrication de celui-ci
WO2019131035A1 (fr) * 2017-12-26 2019-07-04 Ｊｆｅスチール株式会社 Tuyau en acier sans soudure, à résistance élevée et faiblement allié, destiné à des puits de pétrole
WO2020203931A1 (fr) * 2019-03-29 2020-10-08 日鉄ステンレス株式会社 Raccord soudé en acier inoxydable duplex et son procédé de fabrication
WO2021019909A1 (fr) * 2019-07-31 2021-02-04 Ｊｆｅスチール株式会社 Plaque en acier inoxydable duplex austénitique-ferritique

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005179699A (ja) * 2003-12-16 2005-07-07 Nippon Steel Corp ステンレス鋼の電位貴化抑制方法
CN103741056A (zh) * 2014-01-26 2014-04-23 北京科技大学 一种耐南海海洋环境用耐蚀钢板及其生产工艺
JP2017190522A (ja) * 2016-04-11 2017-10-19 Ｊｆｅスチール株式会社 鋼材
WO2019035329A1 (fr) * 2017-08-15 2019-02-21 Ｊｆｅスチール株式会社 Tuyau sans soudure en acier inoxydable hautement résistant pour puits de pétrole, et procédé de fabrication de celui-ci
WO2019131035A1 (fr) * 2017-12-26 2019-07-04 Ｊｆｅスチール株式会社 Tuyau en acier sans soudure, à résistance élevée et faiblement allié, destiné à des puits de pétrole
WO2020203931A1 (fr) * 2019-03-29 2020-10-08 日鉄ステンレス株式会社 Raccord soudé en acier inoxydable duplex et son procédé de fabrication
WO2021019909A1 (fr) * 2019-07-31 2021-02-04 Ｊｆｅスチール株式会社 Plaque en acier inoxydable duplex austénitique-ferritique

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