EP2902525A1 - Duplexedelstahl - Google Patents

Duplexedelstahl Download PDF

Info

Publication number
EP2902525A1
EP2902525A1 EP15156371.5A EP15156371A EP2902525A1 EP 2902525 A1 EP2902525 A1 EP 2902525A1 EP 15156371 A EP15156371 A EP 15156371A EP 2902525 A1 EP2902525 A1 EP 2902525A1
Authority
EP
European Patent Office
Prior art keywords
less
mass
duplex stainless
stainless steel
content
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP15156371.5A
Other languages
English (en)
French (fr)
Other versions
EP2902525B1 (de
Inventor
Hisashi Amaya
Hideki Takabe
Kazuhiro Ogawa
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Nippon Steel and Sumitomo Metal Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumitomo Metal Corp
Publication of EP2902525A1 publication Critical patent/EP2902525A1/de
Application granted granted Critical
Publication of EP2902525B1 publication Critical patent/EP2902525B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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 ferrite-austenite duplex stainless steel excellent in stress corrosion cracking resistance, in particular to a duplex stainless steel suitable as a steel material for line pipes transporting petroleum, natural gas or the like.
  • duplex stainless steels composed of ferrite-austenite phases
  • Patent Document 1 describes a duplex stainless steel containing Cu in a content of 1 to 3% and improved in corrosion resistance in chloride and sulfide environments.
  • Patent Document 2 describes a duplex stainless steel in which the strength, toughness and seawater resistance are improved by appropriately regulating the contents of Cr, Ni, Cu, Mo, N and W and by controlling the area fraction of the ferrite phase to 40% through 70%.
  • the degradation of the corrosion resistance of the weld zone tends to occur during large heat input welding.
  • intermetallic compounds precipitate in the weld zone during large heat input welding, and hence embrittlement and degradation of the corrosion resistance tend to occur in the weld zone, and additionally, on the assumption of the transportation of petroleum or natural gas, insufficient is the stress corrosion cracking resistance in a chloride environment containing corrosive associated gases such as carbon dioxide gas and hydrogen sulfide.
  • the present invention has been performed for the purpose of solving the aforementioned problems, and an object of the present invention is to provide a duplex stainless steel excellent in the weldability during large heat input welding and excellent in the stress corrosion cracking resistance in the chloride environment containing corrosive associated gases.
  • the present inventors performed a series of various experiments and detailed studies for the purpose of actualizing in a duplex stainless steel the improvement of the weldability during large heat input welding and the improvement of the stress corrosion cracking resistance in the chloride environment. Consequently, the present inventors have obtained the following findings (a) to (f).
  • Figure 4 is a graph in which for duplex stainless steels having various chemical compositions, used in Examples described later, the content (mass%) of "Cr” is plotted on the X-axis and the content (mass%) of "7Mo + 3Cu” is plotted on the Y-axis.
  • the passivation film can be strengthened: 2.2 ⁇ Cr + 7 ⁇ Mo + 3 ⁇ Cu > 66 wherein the symbols of elements in formula (1) respectively represent the contents (unit: mass%) of the elements in the steel.
  • Ni has only not to be contained.
  • the ratio between the ferrite phase and the austenite phase largely deviates from 1:1, and the toughness and the corrosion resistance are degraded. Accordingly, for the purpose of suppressing the production of the sigma phase while the degradation of the toughness and the degradation of the corrosion resistance are being prevented, Ni is required to be contained in an appropriate content depending on the contents of Cu and N.
  • the production of the sigma phase can be suppressed without degrading the toughness and the corrosion resistance: Cr + 11 ⁇ Mo + 10 ⁇ Ni ⁇ 12 ⁇ Cu + 30 ⁇ N wherein the symbols of elements in formula (2) respectively represent the contents (unit: mass%) of the elements in the steel.
  • the left hand side of formula (2) represents the driving force for the precipitation of the sigma phase; among the components constituting the duplex stainless steel, Cr, Mo and Ni are the elements to increase the driving force for the nucleation of the precipitation of the sigma phase; on the basis of various tests, it has been found that the degrees of contribution of Mo and Ni are 11 times and 10 times the degree of contribution of Cr, respectively.
  • the manifestation mechanism of the deterrent force against the precipitation of the sigma phase due to Cu and N is as follows.
  • the presence of a Cu atom or an N atom in the vicinity of each of the Ni atoms present in the crystal lattice suppresses the decrease of the interface energy in the ferrite/austenite phase interface, which is the site of the nucleation of the sigma phase; thus, the decrease amount of the free energy at the time of the precipitation reaction of the sigma phase is made small, and hence the driving force for the crystal nucleation can be made small to be associated with the aforementioned manifestation mechanism.
  • the nuclear growth of the sigma phase can be suppressed by containing an appropriate amount of Cu.
  • an appropriate amount of Cu enables the precipitation of an ultrafine Cu concentrated phase in the matrix during large heat input welding.
  • the Cu concentrated phase serves as the nucleation site of the sigma phase, and hence by precipitating a large number of Cu concentrated phases in a dispersed manner, the Cu concentrated phases can be made to compete against the ferrite phase/austenite phase interface, which is the proper nucleation site. Consequently, the growth of the sigma phase in the ferrite phase/austenite phase interface can be retarded.
  • the present invention has been perfected on the basis of the aforementioned findings, and the gist of the present invention resides in the following items (1) to (4) regarding duplex stainless steel.
  • the duplex stainless steel according to the present invention is excellent in the weldability during large heat input welding and excellent in the stress corrosion cracking resistance in a chloride environment.
  • C is an element effective in stabilizing the austenite phase.
  • carbides tend to precipitate, and the corrosion resistance is degraded. Accordingly, the content of C is set at 0.03% or less.
  • Si is able to ensure the fluidity of the molten metal during welding, and hence is an element effective in preventing weld defects.
  • Si is required to be contained in a content of 0.2% or more.
  • the content of Si exceeds 1%, intermetallic compounds (such as the sigma phase) tend to be produced. Accordingly, the content of Si is set at 0.2 to 1%.
  • the content of Si is preferably 0.2 to 0.5%.
  • Mn is a component effective in improving the hot workability through the desulfurization and deoxidation effects during melting of the duplex stainless steel. Mn also has a function to increase the solubility of N. However, when the content of Mn exceeds 5.0%, the corrosion resistance is degraded. Accordingly, the content of Mn is set at 5.0% or less.
  • the content of P is set at 0.040% or less.
  • Al is a component effective as a deoxidizer of the steel.
  • the content of N in the steel is large, Al precipitates as AlN (aluminum nitride), and degrades the toughness and the corrosion resistance of the steel. Accordingly, the content of Al is set at 0.040% or less.
  • the content of Al as referred to in the present invention means the content of acid-soluble Al (what is called sol. Al).
  • Al is used as a deoxidizer in the duplex stainless steel according to the present invention, because the content of Si as a component effective deoxidizer is suppressed , and hence. However, when the duplex stainless steel is produced by vacuum melting, it is not necessary to contain Al.
  • Ni is a component effective in stabilizing austenite.
  • the content of Ni exceeds 8%, the resultant decrease of the amount of ferrite makes it difficult to ensure the fundamental properties of the duplex stainless steel and also facilitates the production of intermetallic compounds (such as the sigma phase).
  • the content of Ni is less than 4%, the amount of ferrite comes to be too large and thus the features of the duplex stainless steel are lost.
  • the solubility of N in ferrite is small, and hence due to the amount of ferrite becoming too large, nitrides precipitate and the corrosion resistance is degraded. Accordingly, the content of Ni is set at 4 to 8%.
  • Cr is a component effective in maintaining the corrosion resistance.
  • Cr is required to be contained in a content of 20% or more.
  • the content of Cr exceeds 28%, the precipitation of intermetallic compounds (such as the sigma phase) comes to be remarkable, and the degradation of the hot workability and the degradation of the weldability are caused. Accordingly, the content of Cr is set at 20 to 28%.
  • Mo is an element extremely effective in improving the SCC resistance.
  • Mo is required to be contained in a content of 0.5% or more.
  • the content of Mo exceeds 2.0%, the precipitation of intermetallic compounds is remarkably accelerated during large heat input welding, and the degradation of the hot workability and the degradation of the weldability are caused. Accordingly, the content of Mo is set at 0.5 to 2.0%.
  • the content of Mo is preferably 0.7 to 1.8% and more preferably 0.8 to 1.5%.
  • Cu is a component effective in strengthening the passivation film mainly composed of Cr in a chloride environment containing corrosive acidic gasses (such as carbon dioxide gas and hydrogen sulfide gas). Additionally, Cu precipitates in the matrix in an ultrafine manner during large heat input welding to become nucleation sites of intermetallic compounds (the sigma phase) so as to compete against the ferrite/austenite phase interface which is the proper nucleation site. Consequently, there occurs retardation of the sigma phase production, otherwise fast in growth, in the ferrite/austenite phase interface. For the purpose of obtaining these effects, Cu is required to be contained in a content exceeding 2.0%. On the other hand, when Cu is contained in a content exceeding 4.0%, the hot workability of the steel is impaired. Accordingly, the content of Cu is set to be more than 2.0% and 4.0% or less.
  • N is a powerful austenite former, and is effective in improving the thermal stability and the corrosion resistance of the duplex stainless steel.
  • the duplex stainless steel according to the present invention contains Cr and Mo, which are ferrite formers, in large amounts, and hence N is required to be contained in a content of 0.1% or more for the purpose of establishing an appropriate balance between ferrite and austenite.
  • the content of N exceeds 0.35%, the toughness and the corrosion resistance of the steel are degraded due to the occurrence of blow holes as weld defects, the nitride production caused by the thermal effects during welding or the like. Accordingly, the content of N is set at 0.1 to 0.35%.
  • the contents of Cr and Mo are regulated for the purpose of suppressing the precipitation of the intermetallic compounds. Accordingly, for the purpose of strengthening the passivation film mainly composed of Cr, Cu is required to be contained in an appropriate amount in addition to Mo.
  • the value of "2.2Cr + 7Mo + 3Cu" is 66 or less, a sufficient resistance against the stress corrosion cracking (SCC) in a chloride environment cannot be ensured as the case may be. Accordingly, the requirement of the above presented formula (1) is specified.
  • the duplex stainless steel according to the present invention may contain, in addition to the aforementioned elements, one or more of the elements selected from at least one group of the following first to third groups.
  • the content of each of these elements exceeds 0.02%, there is an adverse possibility that the amount of nonmetallic inclusions (such as the oxides and sulfides of Ca, Mg or B) is increased and such inclusions offer the origins of pitting and the degradation of the corrosion resistance occurs. Accordingly, when these elements are contained, the content of each of these elements is set at 0.02% or less. When two selected from among Ca, Mg and B are contained, the upper limit of the total content is 0.04%; and when three of Ca, Mg and B are contained, the upper limit of the total content is 0.06%.
  • Ca, Mg or B For the purpose of stably displaying the improvement effect of the hot workability due to Ca, Mg or B, it is preferable to contain Ca, Mg and B each alone or in total, in a content of "S(mass%) + (1/2) ⁇ O(mass%)" or more.
  • REM may be contained if necessary.
  • a rare earth metal also has an effect to fix S or O to enable further improvement of the hot workability of the duplex stainless steel.
  • the content of the rare earth metal exceeds 0.2%, there is an adverse possibility that the amount of nonmetallic inclusions (such as the oxides and sulfides of the rare earth metal) is increased and such inclusions offer the origins of pitting and the degradation of the corrosion resistance occurs. Accordingly, when the rare earth metal is contained, the content of the rare earth metal is set at 0.2% or less.
  • each of the plate materials was again heated to 1250°C, and rolled so as to have a thickness of 15 mm by hot rolling (the working temperature: 1050°C or higher); then each of the plate materials after rolling was subjected to a solid solution heat treatment (a treatment of water cooling after being maintained in a soaked manner at 1070°C for 30 minutes) to prepare a test steel plate.
  • a solid solution heat treatment a treatment of water cooling after being maintained in a soaked manner at 1070°C for 30 minutes
  • Figure 1 shows a plate material 10 which is prepared by mechanical working.
  • (a) is a plan view and (b) is a front view.
  • FIG. 2 for each of the test steels, two pieces of the plate material 10 having a shape shown in Figure 1 were prepared and arranged so as for the groove faces to butt each other; then, a weld joint 20 was prepared by performing multilayer welding based on tungsten inert gas (TIG) welding from the one side of each of the plate materials.
  • Figure 2(a) is a plan view
  • Figure 2(b) is a front view of the weld joint 20.
  • TOG tungsten inert gas
  • FIG. 2(a) is a plan view
  • Figure 2(b) is a front view of the weld joint 20.
  • the welding material 30 of each of the weld joints 20 a welding material of 2 mm in outer diameter prepared from the Test No. 1 in Table 1 was used commonly for all the test steels. The welding was performed under the condition of the heat input amount of 30 kJ/cm, which was particularly highly efficient for a common welding working of stainless steel.
  • a duplex stainless steel that has a chemical composition consisting, by mass%, of C: 0.03% or less, Si: 0.2 to 1%, Mn: 5.0% or less, P: 0.040% or less, S: 0.010% or less, sol. Al: 0.040% or less, Ni: 4 to 8%, Cr: 20 to 28%, Mo: 0.5 to 2.0%, Cu: more than 2.0% and 4.0% or less and N: 0.1 to 0.35%, with the balance being Fe and impurities; wherein the duplex stainless steel satisfies the relations of the following formulas (1) and (2): 2.2 ⁇ Cr + 7 ⁇ Mo + 3 ⁇ Cu > 66 Cr + 11 ⁇ Mo + 10 ⁇ Ni ⁇ 12 ⁇ Cu + 30 ⁇ N wherein the symbols of elements in formulas (1) and (2) respectively represent the contents (unit: mass%) of the elements in the steel.
  • the duplex stainless steel according to Embodiment 1 which further contains, by mass%, V: 1.5% or less, in place of part of Fe.
  • the duplex stainless steel according to Embodiment 1 or 2 which further contains, by mass%, one or more selected from among Ca: 0.02% or less, Mg: 0.02% or less and B: 0.02% or less, in place of part of Fe.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Arc Welding In General (AREA)
EP15156371.5A 2009-09-10 2010-09-01 Duplexedelstahl Active EP2902525B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2009209160 2009-09-10
EP10815306.5A EP2476771B1 (de) 2009-09-10 2010-09-01 Zweiphasiger edelstahl

Related Parent Applications (1)

Application Number Title Priority Date Filing Date
EP10815306.5A Division EP2476771B1 (de) 2009-09-10 2010-09-01 Zweiphasiger edelstahl

Publications (2)

Publication Number Publication Date
EP2902525A1 true EP2902525A1 (de) 2015-08-05
EP2902525B1 EP2902525B1 (de) 2016-05-11

Family

ID=43732382

Family Applications (2)

Application Number Title Priority Date Filing Date
EP15156371.5A Active EP2902525B1 (de) 2009-09-10 2010-09-01 Duplexedelstahl
EP10815306.5A Active EP2476771B1 (de) 2009-09-10 2010-09-01 Zweiphasiger edelstahl

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP10815306.5A Active EP2476771B1 (de) 2009-09-10 2010-09-01 Zweiphasiger edelstahl

Country Status (10)

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

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2677056B1 (de) * 2011-02-14 2016-05-18 Nippon Steel & Sumitomo Metal Corporation Duplexedelstahl
CN103370436B (zh) * 2011-02-14 2016-04-20 新日铁住金株式会社 双相不锈钢及其制造方法
BR112014005028B1 (pt) 2011-09-06 2020-01-07 Nippon Steel Corporation Aço inoxidável dúplex
CN104245211B (zh) * 2012-03-30 2018-11-20 新日铁住金株式会社 焊接接头的制造方法
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
CN103602915B (zh) * 2013-11-22 2015-11-18 山东建筑大学 高碳高铬双相不锈钢
CN109072386A (zh) * 2016-06-01 2018-12-21 新日铁住金株式会社 双相不锈钢和双相不锈钢的制造方法
JP6780426B2 (ja) * 2016-10-06 2020-11-04 日本製鉄株式会社 二相ステンレス鋼
JP6946737B2 (ja) * 2017-05-18 2021-10-06 日本製鉄株式会社 二相ステンレス鋼材及びその製造方法
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

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS55158256A (en) * 1979-05-29 1980-12-09 Daido Steel Co Ltd Ferritic-austenitic two-phase stainless steel
GB2166159A (en) * 1983-01-05 1986-04-30 Carpenter Technology Corp Method of enhancing intergranular corrosion resistance of a weld of the stainless duplex ferritic austenitic steel
EP0261345A1 (de) * 1986-08-29 1988-03-30 SANDUSKY FOUNDRY & MACHINE Co. Rostfreier Stahl mit Zweiphasen-Mikrostruktur und guter Beständigkeit gegen Lochfrasskorrosion
US4816085A (en) * 1987-08-14 1989-03-28 Haynes International, Inc. Tough weldable duplex stainless steel wire
WO1996018751A1 (fr) 1994-12-16 1996-06-20 Sumitomo Metal Industries, Ltd. Acier inoxydable duplex presentant une remarquable resistance a la corrosion
JP2000313940A (ja) * 1999-04-27 2000-11-14 Sumitomo Metal Ind Ltd 二相ステンレス鋼材およびその製造方法
WO2001000898A1 (en) * 1999-06-29 2001-01-04 Sandvik Ab; (Publ) Duplex stainless steel
JP2003171743A (ja) 2001-12-06 2003-06-20 Aichi Steel Works Ltd 強度、靭性、耐海水性の優れた二相ステンレス鋼及びその製造方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4604887A (en) * 1984-11-30 1986-08-12 Kawasaki Steel Corporation Duplex stainless steel seamless pipe and a method for producing the same
JP3155431B2 (ja) * 1994-10-26 2001-04-09 株式会社安来製作所 ２相ステンレス鋳造部材およびその製造方法
JPH1060598A (ja) * 1996-08-19 1998-03-03 Nkk Corp 耐海水性用析出強化型二相ステンレス鋼
US6033497A (en) * 1997-09-05 2000-03-07 Sandusky International, Inc. Pitting resistant duplex stainless steel alloy with improved machinability and method of making thereof
JP2004277767A (ja) * 2003-03-13 2004-10-07 Nisshin Steel Co Ltd 自動車の給油管および燃料タンク用オーステナイト系ステンレス鋼並びに自動車の給油管および燃料タンク
JP4915121B2 (ja) * 2006-03-31 2012-04-11 住友金属工業株式会社 二相ステンレス鋼継目無管の製造方法
JP5072285B2 (ja) * 2006-08-08 2012-11-14 新日鐵住金ステンレス株式会社 二相ステンレス鋼
JP5171197B2 (ja) * 2007-10-10 2013-03-27 新日鐵住金ステンレス株式会社 冷間鍛造性に優れた高強度・高耐食ボルト用２相ステンレス鋼線材、鋼線およびボルト並びにその製造方法
CN103370436B (zh) * 2011-02-14 2016-04-20 新日铁住金株式会社 双相不锈钢及其制造方法
EP2677056B1 (de) * 2011-02-14 2016-05-18 Nippon Steel & Sumitomo Metal Corporation Duplexedelstahl

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS55158256A (en) * 1979-05-29 1980-12-09 Daido Steel Co Ltd Ferritic-austenitic two-phase stainless steel
GB2166159A (en) * 1983-01-05 1986-04-30 Carpenter Technology Corp Method of enhancing intergranular corrosion resistance of a weld of the stainless duplex ferritic austenitic steel
EP0261345A1 (de) * 1986-08-29 1988-03-30 SANDUSKY FOUNDRY & MACHINE Co. Rostfreier Stahl mit Zweiphasen-Mikrostruktur und guter Beständigkeit gegen Lochfrasskorrosion
US4816085A (en) * 1987-08-14 1989-03-28 Haynes International, Inc. Tough weldable duplex stainless steel wire
WO1996018751A1 (fr) 1994-12-16 1996-06-20 Sumitomo Metal Industries, Ltd. Acier inoxydable duplex presentant une remarquable resistance a la corrosion
JP2000313940A (ja) * 1999-04-27 2000-11-14 Sumitomo Metal Ind Ltd 二相ステンレス鋼材およびその製造方法
WO2001000898A1 (en) * 1999-06-29 2001-01-04 Sandvik Ab; (Publ) Duplex stainless steel
JP2003171743A (ja) 2001-12-06 2003-06-20 Aichi Steel Works Ltd 強度、靭性、耐海水性の優れた二相ステンレス鋼及びその製造方法

Also Published As

Publication number Publication date
CA2770378C (en) 2014-02-18
MX352395B (es) 2017-11-22
BR112012005005A2 (pt) 2016-05-03
EP2902525B1 (de) 2016-05-11
BR112012005005B1 (pt) 2023-01-24
JP4640536B1 (ja) 2011-03-02
AU2010293591A1 (en) 2012-03-01
US20120177529A1 (en) 2012-07-12
AU2010293591B2 (en) 2013-01-17
WO2011030709A1 (ja) 2011-03-17
EP2476771A1 (de) 2012-07-18
CN102482746A (zh) 2012-05-30
EP2476771B1 (de) 2015-03-04
JPWO2011030709A1 (ja) 2013-02-07
MX2012002870A (es) 2012-04-20
EP2476771A4 (de) 2014-07-23
CN102482746B (zh) 2016-06-22
CA2770378A1 (en) 2011-03-17
IN2012DN01250A (de) 2015-05-15

Similar Documents

Publication Publication Date Title
EP2902525B1 (de) Duplexedelstahl
JP6437062B2 (ja) クラッド鋼用二相ステンレス鋼及びクラッド鋼
US8137613B2 (en) Austenitic stainless steel welded joint and austenitic stainless steel welding material
EP2677056B1 (de) Duplexedelstahl
US9579870B2 (en) Welded joint of duplex stainless steel
EP2677054A1 (de) Duplex-edelstahl und herstellungsverfahren dafür
EP2412841B1 (de) Austenitischer edelstahl
JP5370537B2 (ja) 溶接構造物用マルテンサイト系ステンレス鋼
EP2754726B1 (de) Zweiphasiger edelstahl
KR20090078813A (ko) 듀플렉스 스테인리스 강 합금 및 이 합금의 용도
US20190126408A1 (en) Welding Structure Member
EP3437790A1 (de) Geschweisstes strukturelement
EP4234739A1 (de) Schweissverbindung aus rostfreiem zweiphasenstahl
US20210292876A1 (en) Austenitic Heat Resistant Alloy and Welded Joint Including the Same
JP2021080510A (ja) オーステナイト系耐熱鋼溶接継手

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20150224

AC Divisional application: reference to earlier application

Ref document number: 2476771

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

17P Request for examination filed

Effective date: 20150814

RBV Designated contracting states (corrected)

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20151120

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AC Divisional application: reference to earlier application

Ref document number: 2476771

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 798728

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160515

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602010033411

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: NO

Ref legal event code: T2

Effective date: 20160511

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 798728

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160511

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160912

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160812

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602010033411

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160511

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20170214

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20170531

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160930

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160901

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160930

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160901

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20100901

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160930

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160511

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 602010033411

Country of ref document: DE

Representative=s name: ZIMMERMANN & PARTNER PATENTANWAELTE MBB, DE

Ref country code: DE

Ref legal event code: R081

Ref document number: 602010033411

Country of ref document: DE

Owner name: NIPPON STEEL CORPORATION, JP

Free format text: FORMER OWNER: NIPPON STEEL & SUMITOMO METAL CORPORATION, TOKYO, JP

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20190814

Year of fee payment: 10

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NO

Payment date: 20190910

Year of fee payment: 10

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20200819

Year of fee payment: 11

REG Reference to a national code

Ref country code: NO

Ref legal event code: MMEP

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20201001

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20201001

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NO

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200930

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20210901

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210901

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20230810

Year of fee payment: 14

Ref country code: DE

Payment date: 20230802

Year of fee payment: 14