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WO2025206331A1 - Tôle en acier inoxydable duplex d'austénite ferritique et son procédé de production - Google Patents

Tôle en acier inoxydable duplex d'austénite ferritique et son procédé de production

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Publication number
WO2025206331A1
WO2025206331A1 PCT/JP2025/012832 JP2025012832W WO2025206331A1 WO 2025206331 A1 WO2025206331 A1 WO 2025206331A1 JP 2025012832 W JP2025012832 W JP 2025012832W WO 2025206331 A1 WO2025206331 A1 WO 2025206331A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
stainless steel
duplex stainless
ferritic
steel sheet
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.)
Pending
Application number
PCT/JP2025/012832
Other languages
English (en)
Japanese (ja)
Inventor
真知 川
雄介 及川
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 Corp
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Filing date
Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of WO2025206331A1 publication Critical patent/WO2025206331A1/fr
Pending legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • Duplex stainless steel is a stainless steel that has both austenite and ferrite phases in its structure. Compared to austenitic stainless steel, which generally has the same corrosion resistance, duplex stainless steel has a low Ni content, making it cheaper to alloy and higher in strength. As such, it has attracted attention as a material that combines strength and corrosion resistance at low cost.
  • SUS304N2 which contains nitrogen (N) to enhance hardness
  • N nitrogen
  • Patent Documents 1 and 2 disclose a method for producing a duplex stainless steel having excellent wear resistance and weld corrosion resistance and a surface hardness of HBW 230 or more by hot rolling a duplex stainless steel having a PRE W,Mn of 24.0 or more and 34.0 or less at a finish rolling temperature of 1000 to 800°C and a cooling rate of 1°C/s or more in the 800 to 600°C range.
  • Patent Document 3 discloses a method for producing ferritic-martensitic duplex stainless steel with excellent abrasive wear resistance and a Brinell hardness of 300 or more.
  • Patent Documents 1 and 2 disclose methods for producing duplex stainless steels with good surface hardness and weld corrosion resistance by low-temperature finishing. However, while these documents mention surface hardness, they do not mention abrasive wear resistance.
  • the objective of the present invention is to provide a ferritic-austenitic duplex stainless steel sheet with excellent abrasive wear resistance and corrosion resistance, and a method for manufacturing the same.
  • the inventors manufactured steel plates from duplex stainless steels containing various chemical compositions by varying the rolling conditions, and evaluated the factors that affect the abrasive wear resistance of the steel plates. In particular, they focused on the ease with which the austenite phase undergoes deformation-induced martensitic transformation, and investigated factors that improve abrasive wear resistance, resulting in the following findings.
  • the present invention was made based on the above findings and includes the following aspects.
  • a ferritic-austenitic duplex stainless steel plate The chemical composition of the ferritic-austenitic duplex stainless steel plate is, in mass%, C: 0.050% or less, Si: 2.00% or less, Mn: 0.5-6.0%, P: 0.0500% or less, S: 0.0500% or less, N: 0.08-0.30%, Cr: 17.0-30.0%, Ni: 0.1 to 8.0%, Mo: 0.1 to 3.5%, Cu: 0 to 3.0% Nb: 0 to 0.100%, Sn: 0-1.00%, W: 0-1.00%, V: 0 to 1.00%, Ti: 0 to 0.050%, B: 0 to 0.0050%, Ca: 0-0.0050%, Mg: 0 to 0.0050%, Al: 0 to 0.0500%, and REM: 0 to 0.500% and the balance being Fe and impurities,
  • the PREN_Mn value calculated by the following formula 1 is 35.0 or less, the area fraction of the austenite phase at
  • the average KAM value of the austenite phase at a position 0.5 mm from the surface of the ferritic-austenitic duplex stainless steel plate in the plate thickness direction is 1.0° or more;
  • a ferric chloride CPT test in accordance with ASTM G48E method is carried out on the ferritic-austenitic duplex stainless steel plate and a sample obtained by subjecting the ferritic-austenitic duplex stainless steel plate to a solution heat treatment at 1050°C for 5 minutes, and the difference in ferric chloride CPT between the ferritic-austenitic duplex stainless steel plate and the solution heat treated sample is 10°C or less;
  • a test piece having dimensions of 8 ⁇ 110L was taken from the ferritic-austenitic duplex stainless steel plate at a position one-quarter of the plate thickness, and the test piece was heated to 1360°C at 30°C/s by high-frequency heating with a soaking zone of 15 mm and inert gas cooling, followed by 5-second soaking, followed by cooling to
  • a critical pitting temperature (electrochemical CPT) test based on JIS G0590 was conducted on a cross section of the test piece obtained by halving the soaking zone, and the critical pitting temperature of the ferritic-austenitic duplex stainless steel plate and a heat-treated ferritic-austenitic duplex stainless steel plate was found to be 15°C or less.
  • the chemical composition is, in mass %, Cu: 0.1 to 3.0%, Nb: 0.010-0.100%, Sn: 0.03-1.00%, W: 0.01 to 1.00%, and V: 0.01 to 1.00%
  • the chemical composition is, in mass %, Ti: 0.005 to 0.050%, and B: 0.0003 to 0.0050%
  • the chemical composition is, in mass %, Ca: 0.0001-0.0050%, Mg: 0.0001 to 0.0050%, Al: 0.0030 to 0.0500%, and REM: 0.005 to 0.500%
  • the DF value calculated by the following formula 3 is 70 or less, The ferritic-austenite duplex stainless steel sheet according to any one of [1] to [4], wherein the Md30_ ⁇ value calculated by the following formula 4 is ⁇ 150°C or higher.
  • the chemical composition, in mass%, is C: 0.050% or less, Si: 2.00% or less, Mn: 0.5-6.0%, P: 0.0500% or less, S: 0.0500% or less, N: 0.08-0.30%, Cr: 17.0-30.0%, Ni: 0.1 to 8.0%, Mo: 0.1 to 3.5%, Cu: 0 to 3.0% Nb: 0 to 0.100%, Sn: 0-1.00%, W: 0-1.00%, V: 0 to 1.00%, Ti: 0 to 0.050%, B: 0 to 0.0050%, Ca: 0-0.0050%, Mg: 0 to 0.0050%, Al: 0 to 0.0500%, and REM: 0 to 0.500% and the balance being Fe and impurities, is hot-rolled at a rolling reduction of 10% to 40% at 950°C or less to obtain a hot-rolled steel sheet
  • the inclusion of C is not essential, and the C content may be 0%. Since lowering the C content significantly increases costs in existing steelmaking equipment, the C content may be 0.001% or more, 0.002% or more, 0.003% or more, or 0.005% or more.
  • Si (Si: 2.00% or less) Si is sometimes used as a deoxidizing element or added to improve oxidation resistance. However, a large amount of Si hardens the steel sheet, deteriorating its toughness and workability. Therefore, the Si content is set to 2.00% or less.
  • the Si content may be 1.90% or less, 1.80% or less, 1.60% or less, 1.50% or less, 1.40% or less, 1.30% or less, 1.20% or less, 1.10% or less, or 1.00% or less.
  • the inclusion of Si is not essential for the ferritic-austenitic duplex stainless steel sheet of the present invention, and the Si content may be 0%. Reducing the Si content to a minimum increases the cost of refining the steel, so the Si content may be 0.01% or more, 0.02% or more, 0.03% or more, 0.05% or more, or 0.10% or more.
  • Cu is an element that is very effective in improving sulfuric acid resistance, so it may be contained as needed.
  • the inclusion of Cu is not essential, and the Cu content may be 0%.
  • the Cu content is preferably 0.01% or more.
  • the Cu content may be 0.05% or more, 0.1% or more, 0.2% or more, 0.5% or more, 0.7% or more, or 0.8% or more.
  • a large amount of Cu increases raw material costs and deteriorates hot workability. Therefore, the Cu content is set to 3.0% or less.
  • the Cu content may be 2.8% or less, 2.5% or less, 2.2% or less, 2.0% or less, 1.8% or less, or 1.5% or less.
  • the area fraction of the austenite phase at a position 0.5 mm from the surface of the steel plate in the plate thickness direction is 30 to 70%
  • the area fraction of the austenite phase at a position 0.5 mm from the surface of the steel sheet in the sheet thickness direction is 30 to 70%. If the area fraction of the austenite phase is less than 30%, the amount of deformation-induced martensitic transformation is reduced, and good abrasive wear resistance cannot be obtained.
  • the area fraction of the austenite phase may be 35% or more, or 40% or more.
  • the KAM value is the average of the orientation differences between the six adjacent pixels for each pixel. By performing this calculation so as not to cross the grain boundaries, a distribution map of strain based on local orientation changes within the grain can be obtained.
  • the average KAM value is the average of the KAM values for each pixel.
  • the ferritic-austenite duplex stainless steel sheet of the present invention can be produced by hot rolling steel having the above-described chemical composition at a rolling reduction of 10% to 40% at 950°C or less to form a hot-rolled steel sheet, air-cooling the obtained hot-rolled steel sheet at 830°C or higher for 10 seconds or more, followed by cooling at a cooling rate of 1.0°C/s or more in the temperature range from 800°C to 600°C, and then cold-straightening the hot-rolled steel sheet under conditions such that the 0.2% proof stress after cold straightening is 10 MPa or more higher than before cold straightening.
  • hot rolling is carried out at a rolling reduction rate of 10% to 40% at 950°C or below, followed by air cooling at 830°C or above for 10 seconds or more, and then cooling at a rate of 1.0°C/s or more in the temperature range from 800°C to 600°C.
  • hot rolling is performed at a reduction rate of 10% to 40% at 950°C or below.
  • the reduction rate at 950°C or below is a value calculated by (h1-h2)/h1, where h1 is the plate thickness before the initial rolling at 950°C or below and h2 is the plate thickness of the steel sheet. If the reduction rate at 950°C or below is less than 10%, the hot working strain remaining in the steel sheet will be reduced, and the amount of cold straightening required to impart the desired working strain to the austenite phase in the surface layer of the steel sheet will be excessive, making production impossible or significantly increasing production costs.
  • the reduction rate at 950°C or below may be 12% or more, 14% or more, or 15% or more. If the reduction rate at 950°C or below is more than 40%, the residual strain from the hot working will increase, the hot rolling time will be longer, and the temperature of the steel sheet will decrease, resulting in the precipitation of nitrides that deteriorate corrosion resistance during rolling and cooling.
  • the rolling reduction at 950°C or less may be 35% or less, 32% or less, or 30% or less. If the rolling temperature is 950°C or less, the recovery of the austenite phase is sufficiently slow, so a lower limit of the rolling temperature is not specified, but rolling may be performed at 850°C or more, taking into consideration the rolling reaction force and the transportation time to the water cooling device after rolling.
  • the rolling temperature may be 860°C or more, 870°C or more, 880°C or more, 890°C or more, or 900°C or more.
  • the hot-rolled steel sheet is subjected to air cooling at 830°C or higher for 10 seconds or more. Since the ferrite phase recovers at a lower temperature than the austenite phase, air cooling at 830°C or higher for 10 seconds or more can recover only the ferrite phase without recovering the austenite phase. If a large amount of strain remains in the ferrite phase, the strain can accelerate diffusion or become a precipitation site, causing chromium carbonitride to precipitate in the weld HAZ, resulting in deterioration of corrosion resistance.
  • the air cooling time may be 12 seconds or more, 15 seconds or more, 20 seconds or more, 30 seconds or more, or 60 seconds or more.
  • the air cooling time may be, for example, 300 seconds or less, 240 seconds or less, or 180 seconds or less, taking into account manufacturing efficiency.
  • the obtained steel sheet is subjected to cold straightening without solution heat treatment to impart cold working strain.
  • Cold straightening is performed under conditions such that the difference in 0.2% proof stress before and after straightening is 10 MPa or more. If the difference in 0.2% proof stress before and after straightening is less than 10 MPa, sufficient working strain cannot be imparted to the surface layer of the steel sheet, resulting in inferior abrasive wear resistance.
  • the difference in 0.2% proof stress before and after straightening may be 11 MPa or more, 12 MPa or more, 13 MPa or more, or 15 MPa or more.
  • the difference in 0.2% proof stress before and after straightening may be 50 MPa or less, 48 MPa or less, 45 MPa or less, 42 MPa or less, or 40 MPa or less.
  • the method of cold straightening does not matter as long as the 0.2% yield strength increases by 10 MPa or more after cold straightening.
  • Examples of cold straightening methods include leveler straightening. Note that controlling the increase in strength (0.2% yield strength) as an indicator of the degree of cold straightening is a common manufacturing method.
  • the above manufacturing method makes it possible to obtain duplex stainless steel sheets with the aforementioned austenite phase and excellent abrasive wear resistance and corrosion resistance.
  • Example No. 1-1 Steel was melted to produce a 200 mm thick billet having the chemical composition of Composition No. 1 in Table 1.
  • the obtained billet was heated at 1180°C for 60 minutes, hot rolled at a reduction of 25% to 950°C or less, air-cooled at 830°C for 39 seconds, and then cooled from 800°C to 600°C at a rate of 3.2°C/s to obtain a 30 mm thick hot-rolled steel plate.
  • the obtained hot-rolled steel sheet was subjected to cold straightening such that the difference in 0.2% yield strength before and after cold straightening was 38 MPa.
  • the difference in 0.2% yield strength before and after cold straightening was confirmed by conducting tensile tests on samples before and after cold straightening.
  • the area fraction of the austenite phase at a depth of 0.5 mm from the surface, the Md30 value, and the average KAM value were measured, and an abrasive wear test was conducted. Furthermore, a ferric chloride CPT test was conducted on the samples after cold straightening and on samples that had been subjected to solution heat treatment.
  • the area fraction of the austenite phase at a position 0.5 mm from the surface in the sheet thickness direction was measured by embedding a cross section of the steel sheet perpendicular to the rolling direction in resin, etching with a KOH solution to create a contrast between the ferrite phase and the austenite phase, taking a structural photograph of an area of 400 ⁇ m in the direction perpendicular to the sheet thickness direction, with a width of 200 ⁇ m (position 0.4 to 0.6 mm from the surface) in the sheet thickness direction, centered at a position 0.5 mm from the surface, and binarizing the image of the structural photograph.
  • the Md30 value of the austenite phase 0.5 mm from the surface was determined by embedding a cross section of the sample perpendicular to the rolling direction in resin and polishing with colloidal silica. EPMA map analysis was then performed using a beam diameter of 1 ⁇ m and a step size of 1 ⁇ m over an area of 400 ⁇ m perpendicular to the thickness direction, with a width of 200 ⁇ m in the thickness direction (0.4 to 0.6 mm from the surface) centered 0.5 mm from the surface.
  • the average composition of the austenite phase was determined by separating the obtained measurements into austenite and ferrite phases based on the N content and the area fraction of the austenite phase, and the Md30 value of the austenite phase was then calculated using equation 4 above.
  • the steel plate structure may contain precipitates other than nitrides, as well as inclusions that are unavoidably mixed in during the steelmaking process.
  • the total area fraction of these was less than 0.1% at most, and their impact on the calculation of the austenite phase composition was negligible.
  • the average KAM value of the austenite phase 0.5 mm from the surface was calculated by embedding a cross section of the sample perpendicular to the rolling direction in resin and polishing with colloidal silica. EBSD measurements were then performed with a step size of 1 ⁇ m over an area of 400 ⁇ m perpendicular to the thickness direction, with a width of 200 ⁇ m in the thickness direction (0.4 to 0.6 mm from the surface), centered 0.5 mm from the surface. KAM analysis was then performed using the resulting measurement data, with a threshold of 5° and a grain boundary determination of 15°.
  • Wear resistance was evaluated by an abrasive wear test.
  • the abrasive wear test was performed using a 55 mm x 20 mm test piece including the outermost surface of the steel plate, with a steel grid TGC-50 as the wear particles, a test temperature of room temperature, a particle speed of 200 g/min, a particle weight of 12.0 kg, an NBR adhesive foil with an outer diameter of 224 mm x width of 12 mm, a load of 100 N (10.2 kgf), a rotation speed of 50 rpm (sliding speed 0.59 m/s), and a test time of 60 min.
  • Wear resistance was evaluated by comparing it with the abrasive wear amount when a similar test was conducted on SUS304N2.
  • the abrasive wear amount was 6.5 mm 3 /kg or less, which is the abrasive wear amount of SUS304N2
  • the wear resistance was judged to be good and rated as " ⁇ "
  • the wear resistance was judged to be poor and rated as " ⁇ "
  • the corrosion resistance of the base material was evaluated by the difference in ferric chloride CPT from a sample that had undergone solution heat treatment. Specifically, a ferric chloride CPT test in accordance with ASTM G48E was carried out on the cold-straightened sample and a sample that had undergone solution heat treatment at 1,050°C for 5 minutes, and the difference in ferric chloride CPT between the solution-treated sample and the cold-straightened sample was taken as the base material CPT difference.
  • base material corrosion resistance if the difference in base material CPT between the sample after cold straightening and the sample after solution heat treatment was 10°C or less, the corrosion resistance was judged to be good and rated as " ⁇ ". If the difference in CPT was more than 10°C, the corrosion resistance was judged to be poor and rated as " ⁇ ".
  • HAZ corrosion resistance The HAZ corrosion resistance was evaluated by the electrochemical CPT difference between the cold-straightened steel sheet and a sample that had been subjected to heat treatment simulating the HAZ of SAW welding. Specifically, a test piece with an 8 ⁇ 110L diameter was taken from the thickness-quarter portion of the cold-straightened sample, and the sample was heated to 1360°C at 30°C/s by high-frequency heating with a soaking zone of 15 mm and inert gas cooling, soaked for 5 seconds, cooled to 900°C at 40°C/s, immediately cooled to 600°C at 11°C/s, and then immediately cooled to 300°C at 2°C/s.
  • HAZ corrosion resistance if the difference in HAZ CPT between the cold-straightened sample and the solution heat-treated sample was 15°C or less, the corrosion resistance was judged to be good and rated as " ⁇ ", and if the difference in CPT was more than 15°C, the corrosion resistance was judged to be poor and rated as " ⁇ ".
  • Table 3 shows the evaluation results for samples 1-1 to 16-3.
  • ⁇ phase ratio refers to the austenite phase ratio (%) measured by image analysis
  • ⁇ phase Md30 refers to the Md30 value (°C) calculated from the composition of the austenite phase measured by EPMA
  • ⁇ phase KAM refers to the average KAM value of the austenite phase measured by EBSD.
  • sample number 4-4 the air cooling time above 830°C was short, which is thought to have caused chromium nitride to precipitate during the simulated welding heat treatment. As a result, HAZ corrosion resistance was reduced.
  • sample number 10-4 the air cooling time above 830°C was short, which is thought to have caused chromium nitride to precipitate during the simulated welding heat treatment. As a result, HAZ corrosion resistance was reduced.
  • the Md30_ ⁇ value was less than -150°C, which is thought to be why the Md30 value of the austenite phase 0.5 mm from the surface of the steel plate in the thickness direction was low. As a result, wear resistance was reduced.
  • the other sample was an example of the present invention, and a duplex stainless steel plate was obtained that combined good corrosion resistance and abrasive wear resistance.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

La présente invention concerne une tôle en acier inoxydable duplex d'austénite ferritique présentant des propriétés exceptionnelles de résistance à la corrosion et de résistance à l'usure par abrasion, et son procédé de production. Une tôle en acier inoxydable duplex d'austénite ferritique selon la présente invention présente une composition chimique prédéfinie et est conçue de telle sorte que : la valeur PREN_Mn calculée en tant que Cr + 3,3 (Mo + 0,5 W) + 16N − Mn est inférieure ou égale à 35,0 ; la fraction surfacique d'une phase austénitique à une position de 0,5 mm dans la direction de l'épaisseur de la tôle à partir de la surface de la tôle en acier est de 30 à 70 % ; la valeur Md30 calculée en tant que valeur Md30 (°C) = 551 − 462 (C + N) − 9,2 Si − 8,1 Mn − 13,7 Cr − 29 (Ni + Cu) − 18,5 Mo − 68 Nb à partir de la composition dans la phase austénitique à la position de 0,5 mm dans la direction de l'épaisseur de la tôle à partir de la surface de la tôle en acier est supérieure ou égale à −150 °C ; la valeur KAM moyenne de la phase austénitique à la position de 0,5 mm dans la direction de l'épaisseur de la tôle à partir de la surface de la tôle en acier est supérieure ou égale à 1,0° ; la différence de chlorure ferrique CPT entre la tôle en acier et la tôle en acier soumise à un traitement thermique en solution solide est inférieure ou égale à 10 °C ; et la différence de température de résistance à la corrosion par piqûration critique entre la tôle en acier et la tôle en acier soumise au traitement thermique est inférieure ou égale à 15 °C.
PCT/JP2025/012832 2024-03-28 2025-03-28 Tôle en acier inoxydable duplex d'austénite ferritique et son procédé de production Pending WO2025206331A1 (fr)

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Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06116684A (ja) * 1992-10-06 1994-04-26 Sumitomo Metal Ind Ltd 耐食性、相安定性に優れた二相ステンレス鋼
JP2012197509A (ja) * 2011-03-09 2012-10-18 Nippon Steel & Sumikin Stainless Steel Corp 溶接部耐食性に優れた二相ステンレス鋼
JP2017145460A (ja) * 2016-02-17 2017-08-24 新日鐵住金ステンレス株式会社 低温での耐破壊性に優れた構造部材用フェライト・オーステナイト系ステンレス鋼板及びその製造方法
JP2019218613A (ja) * 2018-06-21 2019-12-26 日鉄ステンレス株式会社 フェライト・オーステナイト二相ステンレス鋼板および溶接構造物、ならびにそれらの製造方法
JP2021075771A (ja) * 2019-11-12 2021-05-20 日鉄ステンレス株式会社 二相ステンレス鋼および溶接構造物
JP2021167445A (ja) * 2020-04-10 2021-10-21 日本製鉄株式会社 二相ステンレス鋼材
JP2023082763A (ja) * 2021-12-03 2023-06-15 日鉄ステンレス株式会社 クラッド鋼板およびその製造方法
JP2023144574A (ja) * 2022-03-28 2023-10-11 日鉄ステンレス株式会社 フェライト・オーステナイト二相ステンレス鋼板とその製造方法

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06116684A (ja) * 1992-10-06 1994-04-26 Sumitomo Metal Ind Ltd 耐食性、相安定性に優れた二相ステンレス鋼
JP2012197509A (ja) * 2011-03-09 2012-10-18 Nippon Steel & Sumikin Stainless Steel Corp 溶接部耐食性に優れた二相ステンレス鋼
JP2017145460A (ja) * 2016-02-17 2017-08-24 新日鐵住金ステンレス株式会社 低温での耐破壊性に優れた構造部材用フェライト・オーステナイト系ステンレス鋼板及びその製造方法
JP2019218613A (ja) * 2018-06-21 2019-12-26 日鉄ステンレス株式会社 フェライト・オーステナイト二相ステンレス鋼板および溶接構造物、ならびにそれらの製造方法
JP2021075771A (ja) * 2019-11-12 2021-05-20 日鉄ステンレス株式会社 二相ステンレス鋼および溶接構造物
JP2021167445A (ja) * 2020-04-10 2021-10-21 日本製鉄株式会社 二相ステンレス鋼材
JP2023082763A (ja) * 2021-12-03 2023-06-15 日鉄ステンレス株式会社 クラッド鋼板およびその製造方法
JP2023144574A (ja) * 2022-03-28 2023-10-11 日鉄ステンレス株式会社 フェライト・オーステナイト二相ステンレス鋼板とその製造方法

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