WO2011030709A1 - 二相ステンレス鋼 - Google Patents

二相ステンレス鋼 Download PDF

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Publication number
WO2011030709A1
WO2011030709A1 PCT/JP2010/064953 JP2010064953W WO2011030709A1 WO 2011030709 A1 WO2011030709 A1 WO 2011030709A1 JP 2010064953 W JP2010064953 W JP 2010064953W WO 2011030709 A1 WO2011030709 A1 WO 2011030709A1
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mass
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stainless steel
duplex stainless
content
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PCT/JP2010/064953
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English (en)
French (fr)
Japanese (ja)
Inventor
尚 天谷
秀樹 高部
小川　和博
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住友金属工業株式会社
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Application filed by 住友金属工業株式会社 filed Critical 住友金属工業株式会社
Priority to IN1250DEN2012 priority Critical patent/IN2012DN01250A/en
Priority to MX2012002870A priority patent/MX2012002870A/es
Priority to EP10815306.5A priority patent/EP2476771B1/en
Priority to JP2010535094A priority patent/JP4640536B1/ja
Priority to CA2770378A priority patent/CA2770378C/en
Priority to AU2010293591A priority patent/AU2010293591B2/en
Priority to CN201080040231.5A priority patent/CN102482746B/zh
Priority to BR112012005005-2A priority patent/BR112012005005B1/pt
Publication of WO2011030709A1 publication Critical patent/WO2011030709A1/ja
Priority to US13/411,761 priority patent/US20120177529A1/en

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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a ferritic / austenitic duplex stainless steel excellent in stress corrosion cracking resistance, and more particularly to a duplex stainless steel suitable as a steel material for line pipes for transporting oil / natural gas.
  • duplex stainless steel composed of a ferrite and austenite phase
  • Patent Document 1 describes a duplex stainless steel containing 1 to 3% of Cu and having improved corrosion resistance in a chloride or sulfide environment.
  • Patent Document 2 describes the strength, toughness, and the like by appropriately adjusting the contents of Cr, Ni, Cu, Mo, N and W and controlling the area ratio of the ferrite phase to 40% to 70%.
  • a duplex stainless steel with improved seawater resistance is described.
  • the corrosion resistance of the welded portion tends to deteriorate during high heat input welding.
  • intermetallic compounds are precipitated in the welded part at the time of high heat input welding, so that the welded part is likely to be embrittled and deteriorated in corrosion resistance. Assuming natural gas transportation, the stress corrosion cracking resistance in a chloride environment containing corrosive accompanying gases such as carbon dioxide and hydrogen sulfide is insufficient.
  • the present invention has been made in order to solve the above-mentioned problems, and is excellent in weldability at the time of large heat input welding and excellent in stress corrosion cracking resistance in a chloride environment containing corrosive gas. It aims to provide stainless steel.
  • the present inventors conducted various experiments and detailed studies on duplex stainless steels in order to improve the weldability during high heat input welding and the stress corrosion cracking resistance in chloride environments. Piled up. As a result, the following findings (a) to (f) were obtained.
  • the stress corrosion cracking resistance of the duplex stainless steel can be improved by strengthening a passive film mainly composed of Cr with Mo.
  • a passive film mainly composed of Cr with Mo In order to prevent precipitation of intermetallic compounds during high heat input welding, it is necessary to regulate the contents of Cr and Mo.
  • Cr and Mo contents In a high-temperature chloride environment containing carbon dioxide or hydrogen sulfide, if the Cr and Mo contents are reduced, excellent stress corrosion cracking resistance cannot be obtained in the vicinity of the weld.
  • the passive film containing Cr as a main component can be strengthened by an element different from Mo.
  • Cu is an element having an action of reducing the corrosion rate of the steel material in an acidic environment. Therefore, by adding an appropriate amount of Cu in addition to Cr and Mo, the passive film can be stabilized and the passive film can be strengthened.
  • the passive film can be strengthened by adding Cr, Mo and Cu so as to satisfy the relationship of the following formula (1).
  • each element symbol in Formula (1) represents content (unit: mass%) in each steel of each element.
  • the left side of the formula (2) represents the driving force for precipitation of sigma phase
  • Cr, Mo and Ni among the components constituting the duplex stainless steel, Cr, Mo and Ni have the driving force for nucleation of precipitation of sigma phase.
  • Various elements have been found that Mo and Ni are 11 times and 10 times as much as Cr, respectively, with respect to Cr.
  • Equation (2) represents the sigma phase precipitation deterring force, and its contribution is N 30 times that of Cu, and the driving force of Cr is less than that of Cu. It was found by various tests that the deterrent power is 12 times.
  • the expression mechanism of the deterring power of sigma phase precipitation by Cu and N is as follows.
  • the presence of Cu or N atoms in the vicinity of the Ni atoms present in the crystal lattice suppresses the reduction of the interfacial energy at the ferrite / austenite phase interface, which is the nucleation site of the sigma phase, so during the sigma phase precipitation reaction This is because the amount of decrease in the free energy is reduced and the driving force for crystal nucleation can be reduced.
  • Cu precipitates very finely in the matrix as a Cu-concentrated phase many sigma phase nucleation sites are dispersed and compete with the ferrite / austenite phase interface, which is the original nucleation site. This has the effect of delaying sigma phase formation at the fast-growing ferrite / austenite phase boundary.
  • Nuclear growth of the sigma phase can be suppressed by containing an appropriate amount of Cu.
  • an extremely fine Cu concentrated phase can be precipitated in the matrix during high heat input welding. Since this Cu enriched phase becomes a nucleation site of the sigma phase, by dispersing and precipitating a large number of Cu enriched phases, the Cu enriched phase is converted into the ferrite phase / austenite phase that is the original nucleation site. Can compete with the interface. As a result, the growth of the sigma phase at the ferrite phase / austenite phase interface can be delayed.
  • the present invention has been completed based on the above findings, and the gist thereof lies in the following duplex stainless steels (1) to (4).
  • the duplex stainless steel according to the present invention is excellent in weldability during large heat input welding and excellent in stress corrosion cracking resistance in a chloride environment.
  • C 0.03% or less C is an effective component for stabilizing the austenite phase. However, if the C content exceeds 0.03%, carbides are likely to precipitate, and the corrosion resistance is reduced. Therefore, the C content is 0.03% or less.
  • Si 0.2-1% Since Si can ensure the fluidity of the molten metal during welding, it is an effective component for preventing welding defects. In order to acquire this effect, it is necessary to contain 0.2% or more of Si. On the other hand, when the Si content exceeds 1%, an intermetallic compound (sigma phase or the like) is likely to be generated. Therefore, the Si content is 0.2-1%. A preferable Si content is 0.2 to 0.5%.
  • Mn 5.0% or less Mn is an effective component for improving the hot workability by the desulfurization and deoxidation effects at the time of melting duplex stainless steel. Further, Mn has an effect of increasing the solubility of N. However, if the Mn content exceeds 5.0%, the corrosion resistance decreases. Therefore, the Mn content is 5.0% or less.
  • P 0.040% or less P is mixed as an impurity in the steel and lowers the corrosion resistance and toughness of the steel. Therefore, the content of P is set to 0.040% or less.
  • S 0.010% or less S is mixed as an impurity in the steel and reduces the hot workability of the steel.
  • the sulfide becomes a starting point of pitting corrosion and reduces the pitting corrosion resistance of the steel.
  • the S content is set to 0.010% or less.
  • a preferable S content is 0.007% or less.
  • Al is an effective component as a deoxidizer for steel.
  • AlN aluminum nitride
  • the Al content is 0.040% or less.
  • the Al content referred to in the present invention refers to the content of acid-soluble Al (so-called sol. Al).
  • sol. Al acid-soluble Al
  • Ni 4-8% Ni is an effective component for stabilizing austenite. If the Ni content exceeds 8%, it becomes difficult to secure the basic properties of the duplex stainless steel due to the decrease in the ferrite content, and intermetallic compounds (such as sigma phase) are likely to be generated. On the other hand, if the Ni content is less than 4%, the amount of ferrite becomes too large and the characteristics of the duplex stainless steel are lost. Further, since the solid solubility of N in ferrite is small, when the amount of ferrite becomes too large, nitride precipitates and the corrosion resistance decreases. Therefore, the Ni content is 4 to 8%.
  • Cr 20 to 28% Cr is an effective component for maintaining corrosion resistance. In order to obtain the SCC resistance in a chloride environment, it is necessary to contain 20% or more of Cr. On the other hand, if the Cr content exceeds 28%, precipitation of intermetallic compounds (such as sigma phase) becomes prominent, leading to deterioration of hot workability and weldability. Therefore, the Cr content is 20 to 28%.
  • Mo 0.5-2.0%
  • Mo is a very effective component for improving the SCC resistance. In order to acquire this effect, it is necessary to contain Mo 0.5% or more.
  • Mo content exceeds 2.0%, the precipitation of intermetallic compounds is remarkably accelerated during high heat input welding, resulting in a decrease in hot workability and weldability. Therefore, the Mo content is 0.5 to 2.0%.
  • a preferable Mo content is 0.7 to 1.8%, and a more preferable Mo content is 0.8 to 1.5%.
  • Cu more than 2.0% and 4.0% or less
  • Cu enhances a passive film mainly composed of Cr in a chloride environment containing a corrosive acid gas (carbon dioxide gas, hydrogen sulfide gas, etc.). It is an effective ingredient.
  • Cu precipitates very finely in the matrix during high heat input welding and becomes a nucleation site of an intermetallic compound (sigma phase), and competes with the ferrite / austenite phase interface that is the original nucleation site. As a result, the sigma phase formation at the rapidly growing ferrite / austenite phase interface is delayed. In order to obtain these effects, it is necessary to contain Cu exceeding 2.0%. On the other hand, when Cu is contained exceeding 4.0%, the hot workability of steel is impaired. Therefore, the Cu content is more than 2.0% and 4.0% or less.
  • N 0.1 to 0.35%
  • N is a strong austenite-forming element and is effective in improving the thermal stability and corrosion resistance of the duplex stainless steel. Since the duplex stainless steel according to the present invention contains a large amount of Cr and Mo, which are ferrite forming elements, it is necessary to contain N in an amount of 0.1% or more in order to achieve an appropriate balance between ferrite and austenite. . On the other hand, if the N content exceeds 0.35%, the toughness and corrosion resistance of the steel decrease due to the occurrence of blow holes, which are welding defects, or the formation of nitrides due to the thermal effect during welding. Therefore, the N content is 0.1 to 0.35%.
  • the contents of Cr and Mo are regulated in order to suppress precipitation of intermetallic compounds. Therefore, in order to reinforce the passive film containing Cr as a main component, it is necessary to contain an appropriate amount of Cu separately from Mo.
  • the value of “2.2Cr + 7Mo + 3Cu” is 66 or less, sufficient resistance to stress corrosion cracking (SCC) in a chloride environment may not be ensured. Therefore, the requirement of the above formula (1) is defined.
  • the duplex stainless steel according to the present invention has the chemical composition described above, and the balance is Fe and impurities.
  • impurities are components that are mixed due to various factors in the manufacturing process including raw materials such as ore and scrap when industrially producing duplex stainless steel, and have an adverse effect on the present invention. It means what is allowed in the range.
  • the duplex stainless steel according to the present invention further contains one or more elements selected from at least one of the following first to third groups. May be.
  • Group 1 V: 1.5% or less
  • Group 2 Ca, Mg, B: 0.02% or less
  • Group 3 Rare earth elements (REM): 0.2% or less
  • REM Rare earth elements
  • V 1.5% or less V can be contained as necessary.
  • V is effective in improving the corrosion resistance (particularly in an acidic environment) of the duplex stainless steel. More specifically, crevice corrosion resistance can be improved by containing V in combination with Mo and Cu. However, if the V content exceeds 1.5%, the amount of ferrite increases excessively and the toughness and corrosion resistance may decrease, so the V content is set to 1.5% or less. In order to stably exhibit the effect of improving the corrosion resistance of the duplex stainless steel by V, it is preferable to contain 0.05% or more of V.
  • Second group Ca: not more than 0.02%, Mg: not more than 0.02%, B: not less than 0.02%, one or more selected from Ca, Mg and B is necessary It can be contained according to.
  • Ca, Mg and B have an effect of fixing S (sulfur) or O (oxygen) and improving hot workability, respectively.
  • S sulfur
  • O oxygen
  • the hot workability is good even if Ca, Mg or B is not contained.
  • duplex stainless steel is obtained by containing one or more of Ca, Mg and B. The hot workability of can be further improved.
  • the content of these elements exceeds 0.02%, non-metallic inclusions (such as Ca, Mg or B oxides and sulfides) increase, which causes pitting corrosion and lowers corrosion resistance. There is a fear. Therefore, the content of these elements when contained is 0.02% or less.
  • the upper limit of the total content when containing two of Ca, Mg and B is 0.04%, and the upper limit of the total content when containing three of Ca, Mg and B is 0.06. %.
  • it is contained alone or in total “S (mass%) + 1/2 ⁇ O (mass%)” or more. preferable.
  • Rare earth elements 0.2% or less REM can be contained as necessary. Similarly to Ca, Mg and B, the rare earth element also has the effect of fixing S or O and further improving the hot workability of the duplex stainless steel. On the other hand, if the rare earth element content exceeds 0.2%, non-metallic inclusions (rare earth element oxides, sulfides, etc.) increase, which may cause pitting corrosion and decrease corrosion resistance. Therefore, the rare earth element content in the case of inclusion is 0.2% or less. In order to stably exhibit the effect of improving the hot workability by REM, it is preferable to contain “S (mass%) + 1/2 ⁇ O (mass%)” or more.
  • REM is a general term for 17 elements in which Y and Sc are combined with 15 elements of lanthanoid, and one or more of these elements can be contained. Note that the content of REM means the total content of these elements.
  • the duplex stainless steel according to the present invention can be produced by a production facility and a production method which are usually used for commercial production.
  • a production facility for melting of duplex stainless steel, an electric furnace, an Ar—O 2 mixed gas bottom blowing decarburization furnace (AOD furnace), a vacuum decarburization furnace (VOD furnace), or the like can be used.
  • the molten metal may be cast into an ingot, or may be cast into a rod-shaped billet by a continuous casting method.
  • duplex stainless steels having chemical compositions (invention examples: trial numbers 1 to 11, comparative examples: trial numbers 12 to 25) were melted using a vacuum melting furnace having a capacity of 150 kg. Cast into ingot. Next, each ingot was heated to 1250 ° C. and forged into a plate having a thickness of 40 mm. Thereafter, each plate was again heated to 1250 ° C. and rolled to 15 mm by hot rolling (working temperature 1050 ° C. or higher). Then, each plate material after rolling was subjected to a solution heat treatment (treatment of holding water soaking at 1070 ° C. for 30 minutes and then water-cooling) to obtain test steel plates.
  • a solution heat treatment treatment of holding water soaking at 1070 ° C. for 30 minutes and then water-cooling
  • FIG. 1 the board
  • 1A is a plan view and FIG. 1B is a front view.
  • FIG. 2A is a plan view of the welded joint 20
  • FIG. 2B is a front view.
  • the welding material 30 of each welded joint 20 a welding material having an outer diameter of 2 mm produced from the test steel No. 1 in Table 1 was used in common. Further, the welding was performed under the condition of a heat input of 30 kJ / cm, which is particularly efficient as a general stainless steel welding work.
  • a test piece was collected from the back side (the first layer side of the weld bead) of the welded joint 20 obtained as described above. Specifically, a test piece having a thickness of 2 mm, a width of 10 mm, and a length of 75 mm was collected with the back bead and the scale during welding remaining. In FIG. 2, a region collected as a test piece is indicated by a broken line.
  • FIG. 3 shows a perspective view of the collected test piece 40.
  • an upper surface is a rolling surface (lower surface of the welded joint of FIG. 2).
  • the longitudinal direction of the test piece 40 is a direction orthogonal to the weld line.
  • each test piece 40 is sampled so that one of the two boundary lines between the welding material 30 and the plate material 10 on the surface (rolling surface) of the test piece 40 is located at the center of the surface of the test piece 40. did.
  • a four-point bending test was performed using each obtained test piece.
  • a stress corresponding to the yield stress of the test piece was loaded in a 25 mass% NaCl aqueous solution (150 ° C.) into which 3 MPa of CO 2 was injected.
  • the test time for the 4-point bending test is 720 hours.
  • FIG. 4 is a diagram showing the relationship between “7Mo (mass%) + 3Cu (mass%)” and “Cr (mass%)” for the duplex stainless steels of trial numbers 1, 4, 6, 13, and 20. is there.
  • Table 2 no stress corrosion cracking occurred in the test pieces made from the duplex stainless steels of sample numbers 1, 4 and 6, and the duplex stainless steels of sample numbers 13 and 20 In the test piece prepared from the above, stress corrosion cracking occurs. Therefore, as shown in FIG. 4, the values of “7Mo (mass%) + 3Cu (mass%)” of the duplex stainless steels of trial numbers 1, 4, and 6 and “7Mo” of the duplex stainless steels of trial numbers 13 and 20 are used.
  • 7Mo (mass%) + 3Cu (mass%) ⁇ 2.2Cr (mass%) + 66 (3)
  • the duplex stainless steel satisfying the requirements of the present invention can suppress precipitation of intermetallic compounds during high heat input welding and has excellent stress corrosion resistance in a chloride environment. It turns out that it has crackability.
  • the duplex stainless steel according to the present invention is excellent in weldability during large heat input welding and excellent in stress corrosion cracking resistance in a chloride environment.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
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PCT/JP2010/064953 2009-09-10 2010-09-01 二相ステンレス鋼 WO2011030709A1 (ja)

Priority Applications (9)

Application Number Priority Date Filing Date Title
IN1250DEN2012 IN2012DN01250A (enrdf_load_stackoverflow) 2009-09-10 2010-09-01
MX2012002870A MX2012002870A (es) 2009-09-10 2010-09-01 Acero inoxidable duplex.
EP10815306.5A EP2476771B1 (en) 2009-09-10 2010-09-01 Two-phase stainless steel
JP2010535094A JP4640536B1 (ja) 2009-09-10 2010-09-01 二相ステンレス鋼
CA2770378A CA2770378C (en) 2009-09-10 2010-09-01 Duplex stainless steel
AU2010293591A AU2010293591B2 (en) 2009-09-10 2010-09-01 Two-phase stainless steel
CN201080040231.5A CN102482746B (zh) 2009-09-10 2010-09-01 双相不锈钢
BR112012005005-2A BR112012005005B1 (pt) 2009-09-10 2010-09-01 Aço inoxidável dúplex
US13/411,761 US20120177529A1 (en) 2009-09-10 2012-03-05 Duplex stainless steel

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2009209160 2009-09-10
JP2009-209160 2009-09-10

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US13/411,761 Continuation US20120177529A1 (en) 2009-09-10 2012-03-05 Duplex stainless steel

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WO2011030709A1 true WO2011030709A1 (ja) 2011-03-17

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US (1) US20120177529A1 (enrdf_load_stackoverflow)
EP (2) EP2902525B1 (enrdf_load_stackoverflow)
JP (1) JP4640536B1 (enrdf_load_stackoverflow)
CN (1) CN102482746B (enrdf_load_stackoverflow)
AU (1) AU2010293591B2 (enrdf_load_stackoverflow)
BR (1) BR112012005005B1 (enrdf_load_stackoverflow)
CA (1) CA2770378C (enrdf_load_stackoverflow)
IN (1) IN2012DN01250A (enrdf_load_stackoverflow)
MX (2) MX2012002870A (enrdf_load_stackoverflow)
WO (1) WO2011030709A1 (enrdf_load_stackoverflow)

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WO2013146860A1 (ja) * 2012-03-30 2013-10-03 新日鐵住金株式会社 溶接継手の製造方法及び溶接継手
CN103602915A (zh) * 2013-11-22 2014-02-26 山东建筑大学 高碳高铬双相不锈钢
EP2754726A4 (en) * 2011-09-06 2015-09-09 Nippon Steel & Sumitomo Metal Corp TWO-PHASE STAINLESS STEEL
JP2018059157A (ja) * 2016-10-06 2018-04-12 新日鐵住金株式会社 二相ステンレス鋼
JP2018193591A (ja) * 2017-05-18 2018-12-06 新日鐵住金株式会社 二相ステンレス鋼材及びその製造方法
JP2023151344A (ja) * 2022-03-31 2023-10-16 日鉄ステンレス株式会社 粗製リン酸による耐変色性に優れる二相ステンレス鋼およびそれを使用した粗製リン酸用構造物

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WO2012111536A1 (ja) * 2011-02-14 2012-08-23 住友金属工業株式会社 二相ステンレス鋼およびその製造方法
BR112013017647B1 (pt) * 2011-02-14 2019-03-26 Nippon Steel & Sumitomo Metal Corporation Aço inoxidável duplex para uso em linhas de tubulação
CN103014549B (zh) * 2012-12-26 2015-11-18 振石集团东方特钢股份有限公司 一种高性能双相不锈钢及其加工方法
JP6693561B2 (ja) 2016-06-01 2020-05-13 日本製鉄株式会社 二相ステンレス鋼及び二相ステンレス鋼の製造方法
CN107829029B (zh) * 2017-11-10 2020-02-07 洛阳双瑞特种装备有限公司 一种ZG022Cr22Ni5Mo3N材质双相不锈钢冶炼工艺方法
CN115584443A (zh) * 2021-07-05 2023-01-10 中国石油天然气集团有限公司 一种含铜抗菌双相不锈钢连续管及加工方法

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EP2754726A4 (en) * 2011-09-06 2015-09-09 Nippon Steel & Sumitomo Metal Corp TWO-PHASE STAINLESS STEEL
US10000832B2 (en) 2011-09-06 2018-06-19 Nippon Steel & Sumitomo Metal Corporation Duplex stainless steel
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JP5382266B1 (ja) * 2012-03-30 2014-01-08 新日鐵住金株式会社 溶接継手の製造方法及び溶接継手
JP2014000607A (ja) * 2012-03-30 2014-01-09 Nippon Steel & Sumitomo Metal 溶接継手の製造方法及び溶接継手
CN104245211A (zh) * 2012-03-30 2014-12-24 新日铁住金株式会社 焊接接头的制造方法及焊接接头
US9555496B2 (en) 2012-03-30 2017-01-31 Nippon Steel & Sumitomo Metal Corporation Process for producing welded joint using GMA welding and CO2 as a shielding gas
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JP2018193591A (ja) * 2017-05-18 2018-12-06 新日鐵住金株式会社 二相ステンレス鋼材及びその製造方法
JP2023151344A (ja) * 2022-03-31 2023-10-16 日鉄ステンレス株式会社 粗製リン酸による耐変色性に優れる二相ステンレス鋼およびそれを使用した粗製リン酸用構造物

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