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WO2008007572A1 - PLAQUE EN ACIER INOXYDABLE EN AUSTÉNITE ROULÉE AYANT UNE ÉPAISSEUR SUPÉRIEURE OU ÉGALE À 100 mm ET PROCÉDÉ DE PRODUCTION DE CELLE-CI - Google Patents

PLAQUE EN ACIER INOXYDABLE EN AUSTÉNITE ROULÉE AYANT UNE ÉPAISSEUR SUPÉRIEURE OU ÉGALE À 100 mm ET PROCÉDÉ DE PRODUCTION DE CELLE-CI Download PDF

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Publication number
WO2008007572A1
WO2008007572A1 PCT/JP2007/063186 JP2007063186W WO2008007572A1 WO 2008007572 A1 WO2008007572 A1 WO 2008007572A1 JP 2007063186 W JP2007063186 W JP 2007063186W WO 2008007572 A1 WO2008007572 A1 WO 2008007572A1
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WIPO (PCT)
Prior art keywords
thickness
forging
less
rolling
stainless steel
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Ceased
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PCT/JP2007/063186
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English (en)
Japanese (ja)
Inventor
Yutaka Tadokoro
Shinji Tsuge
Kazuhiro Suetsugu
Yoichi Yamamoto
Toshinori Ohtsubo
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Nippon Steel Stainless Steel Corp
Original Assignee
Nippon Steel and Sumikin Stainless Steel Corp
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Publication date
Application filed by Nippon Steel and Sumikin Stainless Steel Corp filed Critical Nippon Steel and Sumikin Stainless Steel Corp
Priority to EP07767966.0A priority Critical patent/EP2042616B1/fr
Priority to CN200780000850XA priority patent/CN101341271B/zh
Publication of WO2008007572A1 publication Critical patent/WO2008007572A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/026—Rolling
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C22C38/44—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
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a cryogenic austenitic stainless steel sheet for use at a cryogenic temperature of 1550 K or less, which is used as a structural material for a superconducting coil of a nuclear fusion reactor or a structural material for LNG (liquefied natural gas).
  • the present invention relates to a rolled steel sheet having a thickness of 10 Qm or more, which could not be produced conventionally.
  • the structural materials that make up the superconducting coils of fusion reactors which are expected to be the next generation energy source, are non-magnetic and at the same time require high strength characteristics in the superconducting temperature range.
  • superconducting coils are expected to be large-scale devices, so thick plates are essential as structural materials.
  • JISG 4 3 0 4 (2 0 0 5) has provisions for hot rolled stainless steel sheets and strips.
  • the strength is 2 45 N / mm 2 or more
  • the tensile strength is The length is defined as 5 50 N / mm 2 and elongation of 40 or more.
  • the thickness of the material before rolling is limited due to the limitations of the rolling mill, and the reduction ratio is also limited.
  • an austenitic stainless steel for cryogenic structure having a high N and Mn is disclosed.
  • a stainless steel having a thickness of 100 mm or more is disclosed. Not disclosed.
  • JP-A-6 1-5 2 3 5 1 discloses a structural austenitic stainless steel having a high N, M n, and A 1 and extremely low temperature resistance and toughness. Stainless steel with a thickness of 100 mm or more is not disclosed.
  • Japanese Laid-Open Patent Publication No. 2-5 7 6 6 8 discloses a cryogenic austenitic stainless steel containing Nb and having a high Mn and excellent reheat resistance characteristics. Stainless steel of 100 mm or more is not disclosed.
  • Japanese Laid-Open Patent Publication No. 7-3 1 6 6 5 3 discloses a method for producing a stainless steel plate of 100 mm or more with excellent cryogenic properties. The addition of i is not disclosed.
  • the above publication discloses a heat treatment method for obtaining a uniform sized structure over the entire cross section, but does not disclose homogenization by refining the solidified structure.
  • Japanese Laid-Open Patent Publication No. 7-310 1 20 discloses a hot rolling method for 50 mm thick and 100 mm thick austenitic stainless steel thick plates. Is not disclosed.
  • Japanese Patent Application Laid-Open No. 8_10 4 9 20 discloses a method for producing a high-strength austenitic / stainless steel sheet (containing Ti). In this stainless steel sheet, T i is added to refine the solidification structure and prevent surface defects during rolling. However, in the manufacturing method, the solution treatment is omitted, and the above-mentioned publication does not disclose a stainless steel plate having a thickness of 100 mm or more.
  • stainless steel having excellent mechanical properties such as resistance to cold and toughness at low temperatures has been disclosed as a conventional technology.
  • An extremely thick rolled product with excellent properties of 100 mm or more and its manufacturing method are not disclosed.
  • forging Compared with rolling, forging has a smaller material thickness constraint due to the forging machine, can increase the reduction ratio, and can be processed in the direction of increasing plate thickness. Processing strain can be introduced, and as a result, it is easy to obtain a fine recrystallized structure over the entire cross section. However, if everything is finished only by forging, it will result in increased costs and reduced productivity.
  • the present invention relates to a material used at a very low temperature, such as a structural material for a superconducting coil of a nuclear fusion reactor or a structural material for LNG (liquefied natural gas), particularly an extremely thick stainless steel plate of 100 mm or more.
  • the purpose of the present invention is to provide a rolled product having excellent mechanical properties over the entire cross section and a manufacturing method for obtaining the rolled product.
  • the part from the surface to the thickness 1 Z 4 to the thickness 3/4 is It is a part where processing strain is difficult to enter by forging or rolling, and it is difficult to ensure strength and ductility at the part.
  • the present inventors investigated various alloys in detail, and first, by defining the composition, it is said that the minimum required strength and ductility can be ensured even at extremely low temperatures. Obtained knowledge.
  • the elements effective for high strength are adjusted within an appropriate range, and in order to obtain a stable and high effect, It is effective to refine the coagulated tissue by adjustment.
  • the present invention is configured based on this finding, and the gist thereof is as follows.
  • the ⁇ ferrite amount calculated ( ⁇ 5 cal; volume%) defined by the following formula (I) is 7% or more and 4% or less, and consists of the balance iron and inevitable impurities.
  • the area reduction rate (A) of forging is defined as follows. Steel ingot cross-sectional area before forging (thickness x width): A.
  • A (A. One ⁇ ') / ⁇ 0
  • the rolling reduction ratio (R) is defined as follows.
  • Thickness of slab after rolling ⁇
  • the thickness of the steel ingot with a thickness of 500 mm or more is The forging with an area reduction rate of 0.3 or more in the decreasing direction and the forging with an area reduction rate of 0.1 or more in the direction of increasing thickness are alternately performed at least once each, and then the reduction ratio 1.
  • the area reduction rate (C) of forging in the direction of decreasing or increasing thickness is defined as follows.
  • the rolling reduction ratio (R) is defined as follows.
  • Forging here is free forging using a press, but the entire steel ingot Until the predetermined cross-sectional shape is reached, the pressing may be performed in several times on the same surface and the same direction of the steel ingot. In this case, a series of compression processes by pressing in the same plane and in the same direction until the entire steel ingot reaches a predetermined cross-sectional shape is a single forging process.
  • a thick plate having high strength and ductility at a very low temperature and a thickness of 100 mm or more can be obtained.
  • the austenitic stainless steel sheet of the present invention can be applied as a structural material of a superconducting coil for a thermonuclear fusion reactor (ITER), which is expected as a next-generation energy source.
  • ITER thermonuclear fusion reactor
  • the austenitic stainless steel sheet according to the present invention can be applied to large-sized superconducting equipment and structures for LNG (liquefied natural gas), etc. It is expected to contribute greatly to various industrial fields.
  • the present invention has great industrial and social effects.
  • a steel ingot defining a component composition effective for improving strength is forged in the first half of the process and rolled in the second half of the process.
  • an austenitic stainless rolled steel sheet having a thickness of at least 100 mm and excellent in strength and ductility.
  • a coarse solidified structure may remain from the surface layer at a thickness of 14 to 3/4, and the elongation at that location is low, which may limit the strength and ductility balance of the entire cross section. .
  • the balance of strength and ductility is improved by refining the crystal structure of the product over the entire cross section by combining the refinement of the solidification structure by adding Ti and the forging and rolling process. It is characterized by planning.
  • N is an extremely effective element for stabilizing the austenite phase and ensuring strength at cryogenic temperatures. However, if the content is less than 0.1%, the effect is small. If the content exceeds 0.22%, the weldability is significantly deteriorated and weld cracks and blowholes frequently occur. .1 0 or more and 0.22 or less.
  • the strength at cryogenic temperature correlates with the amount of (C + N) in the steel. The more C + N, the higher the strength. For C and N, the content range was specified, so C + N was set to 0.12% or more.
  • Mn is less than 0.1%, the cleanliness of the steel becomes poor. If it exceeds 2.0%, the hot workability deteriorates, so the Mn content is 0.1 or more and 2.0% or less. It was. Cr needs to be 15% or more in order to ensure corrosion resistance when machining parts, but if it exceeds 27%, a brittle sigma phase is generated and toughness deteriorates. Of 15 to 27%.
  • Ni is an element that stabilizes the austenite phase and increases strength, toughness, and ductility at cryogenic temperatures, but if it is less than 8%, the austenite phase stabilization effect is insufficient, so 8% Was the lower limit. However, since it is an extremely expensive element, the upper limit is set to 20%, at which the austenite stabilizing effect is saturated, from the viewpoint of cost.
  • Mo added to ensure strength exceeds 4%, intermetallic compounds such as sigma phase will be generated, and the toughness at cryogenic temperatures will deteriorate, and adding a large amount will increase the cost. Therefore, the Mo content was set to 4% or less. If the content is less than 0.5%, the effect of improving the strength is small, so addition of 0.5% or more is desirable.
  • Co When Co is mixed as an impurity element, it is activated and harmful. In order to reduce activation, the Co content was set to 0.1% or less.
  • Cu is an element that increases corrosion resistance, it is actively added. If it is less than 0.1%, there is no effect, and if it exceeds 3%, hot workability is impaired. Therefore, the Cu content is set to 0.1% or more and 3% or less.
  • a 1 is an element that improves the cleanliness of steel as a deoxidizer. However, if the content is less than 0.001%, this effect is not obtained. If the content exceeds 0.110%, the hot workability deteriorates, so the content of 1 is not less than 0.001 and not more than 0.10%. It was.
  • Ca added for the purpose of improving hot workability is less than 0.0 0 0 5%, and there is no effect of improving hot workability, and if it exceeds 0.0 1%, cleanliness is poor. Therefore, the Ca content is set to 0.0 0 0 5 or more and 0.0 1% or less.
  • T i refines the solidified structure and improves strength and elongation more stably. Add to increase. If the content is less than 0.0%, there is no effect of addition, and if the content exceeds 0.03%, coarse nitrides precipitate and the toughness deteriorates, so the T i content is reduced to 0.01. 0% or more and 0.0 3 0% or less.
  • S contained as an inevitable impurity is an element that lowers hot workability and toughness, and is desirably reduced to 0.03% or less.
  • P contained as an inevitable impurity is an element harmful to corrosion resistance, and is desirably reduced to 0.040% or less.
  • ⁇ 5 cal is the recommended formula of DJK0TECKI & TA SIEWERT (Weld. J., 71 (19 92), 171s) and the recommended formula of TA SIEWERT, N. McCOWAN & DL OLSON (Weld. J., 67 ( 1988), 289s), and represents the ratio of the amount of ⁇ -ferrite in the solidified tissue.
  • the amount of ferrite deposited was estimated by the formula obtained in the experiment for a steel ingot with a small cross section.
  • the ⁇ ferrite amount of the large-section steel ingot targeted by the present invention is about 10% to + 8% higher than the ⁇ ferrite precipitation amount predicted by this formula. confirmed.
  • ⁇ ferrite appears during solidification, it is effective in refining the austenite solidification structure, and ⁇ ferrite is finely dispersed in the steel sheet. If so, crystal grain coarsening during heating is suppressed.
  • S ea l is set to 17% or more and 4% or less.
  • the width direction There are three directions of elongation of the steel sheet: the width direction, the length direction, and the thickness direction.
  • the elongation in the width direction and the length direction was specified.
  • the elongation is set to 30% or more because there is no practical problem if it is 30% or more at any part in the thickness direction at temperatures up to 4 K below room temperature.
  • the elongation is preferably 40% or more.
  • a steel ingot having a thickness of 6500 mm or more is forged at an area reduction ratio of 0.5 or more, then hot-rolled at a reduction ratio of 1.5 or more, and then The technical reason for applying the solution heat treatment will be described.
  • the target steel ingot is limited to steel ingots with a thickness of 6500 mm or more.
  • the area reduction rate was set to 0.5 or more in consideration of introducing sufficient working strain into the fabricated structure over the entire cross section.
  • Hot rolling is a post-forging process until the product thickness is obtained.
  • the reduction ratio is increased as much as possible to introduce strain throughout the entire cross section.
  • the reduction ratio of hot rolling was set to 1.5 or more.
  • the solution heat treatment is performed for the purpose of obtaining sufficient characteristic values for mechanical properties such as strength and elongation, and corrosion resistance by solidifying the constituent elements and making the metal structure and crystal grain size uniform.
  • a steel ingot with a thickness of 6500 mm or more with the composition specified above is forged at an area reduction rate of 0.5 or more, then hot-rolled at a reduction ratio of 1.5 or more, and then solidified.
  • an austenitic stainless rolled steel sheet having an elongation in the width direction and a length direction of 30% or more and a thickness of 100 mm or more at any part in the thickness direction is obtained. Can be manufactured.
  • the area reduction rate (C) of forging in the direction of decreasing or increasing thickness is defined as follows.
  • n Ingot cross-sectional area after first forging (thickness x width):
  • the rolling reduction ratio (R) is defined as follows.
  • the area reduction rate per time in forging in the direction of increasing thickness is less than 0.15, the effect is small, and a uniform structure is obtained at 0.15 or more, so the area reduction rate is 0.15. That's it.
  • the area reduction rate per stroke in forging in the direction of decreasing thickness should be 0.3 or more.
  • Forging in the direction of decreasing thickness and forging in the direction of increasing thickness may be started from either. And it is enough to do it one or more times alternately.
  • forging patterns such as “increase direction, decrease direction, increase direction”, “decrease direction, increase direction, and decrease direction” can be employed.
  • strain By forging from the direction perpendicular to the thickness direction, strain can be applied from two directions, the number of sliding surfaces can be increased, and machining strain can be introduced in all directions from all other directions.
  • the process of forging in the direction of increasing thickness is thought to have had a significant effect on the formation of a uniform structure. In this case, the thickness of the initial steel ingot is also reduced to 500 mm or more. Also, after forging, hot rolling is performed at a reduction ratio of 1.5 or more, and then solution heat treatment is performed, which is the same as described above.
  • Table 1 and Table 4 Steels shown in Table 1 and Table 4 were forged and subjected to forging with a reduction ratio of 1.5, 2.0, and 2.5, and then hot with a reduction ratio of 1.4 to 3.7.
  • a thick plate with a thickness of 100-250 mm was manufactured by applying Shonobu.
  • Tables 2 and 3 show the manufacturing conditions and results of the steels shown in Table 1.
  • Table 5 shows the production conditions and production results of steels No. 1 to 13 of the present invention shown in Table 4 and Comparative Steel Nos. 1 to 11 (claims 1 to 3).
  • Table 6 shows the production conditions and production results of the present invention steels No. 14 to 18 shown in Table 4 and comparative steel Nos. 1 2 to 1: 3 (Claim 4).
  • a thick plate that had been forged and rolled under the production conditions shown in Table 2 was subjected to a solution heat treatment by heating to 110 ° C. and cooling with water.
  • test piece a 14A No. 14A test piece (diameter 6 mm, gauge distance 30 mm, total length 1 1 O mm) of JISZ 2201 was used.
  • the test piece is near the end of the product plate in the longitudinal direction (from the top of the steel ingot From the central part in the width direction (the part corresponding to the center of the width direction of the steel ingot) at the part corresponding to ⁇ 200 mm, the product surface layer (part 10 mm from the surface), and the thickness from the surface layer to 1/4 From the part and the surface layer, it was cut out from the five parts of the part of the plate thickness 1 Z 2, the part of the plate thickness 3 Z 4 and the back surface layer. The strength was evaluated by a tensile test.
  • Tables 2 and 3 show 0.2% resistance to strength, tensile strength, and elongation for typical steels of the present invention. Elongation showed values in the width direction and length direction of the thick plate from the cross-sectional part.
  • the steels shown in Table 4 were 0.2% resistant to strength, tensile strength, and elongation for all examples at the thickness of 1/4 to 3/4 in the same cross section. The lowest value was shown.
  • the inventive steels No. 1 to 13 and the comparative steels No. 1 to 11 were manufactured according to the manufacturing conditions shown in Table 5.
  • Invented steel No. 14 is forged in the forging process before rolling in the width direction of the steel ingot with an area reduction rate of 0.25 and increased in thickness from 73 mm to 900 mm. After that, forging was performed in the thickness direction with an area reduction rate of 0.6, and then rolling with a reduction ratio of 1.8 to obtain a product with a thickness of 200 mm.
  • Invented steel No. 15 is forged in the longitudinal direction of the steel ingot in the forging process before rolling, and is forged at an area reduction rate of 0.15 to increase the thickness from 73 mm to 900 mm. Then, forging at an area reduction rate of 0.6 in the thickness direction, and then rolling at a reduction ratio of 1.8 to obtain a product having a thickness of 200 mm. No.
  • Invented steel No. 17 is a forging process before rolling in the thickness direction of the steel ingot.
  • the thickness was reduced to 3 58 mm, and then rolled at a reduction ratio of 1.8 to obtain a product with a thickness of 200 mm.
  • the invention steel No. 18 is forged in the forging process before rolling in the width direction of the steel ingot with an area reduction rate of 0.25, and the thickness is increased from 500 mm to 6 14 mm. After that, forging at an area reduction rate of 0.6 in the thickness direction, the thickness was reduced to 4 30 mm, and then forging at an area reduction rate of 0.25 in the width direction, the thickness was reduced to 4 7 Increase to 1 mm, then forge in the thickness direction with an area reduction rate of 0.6, reduce the thickness to 3 30 mm, After that, the product was rolled at a reduction ratio of 1.8 to obtain a product with a thickness of 1 84 mm. In comparison steel No. 1 2, the difference in strength due to the difference in forging area reduction rate is compared with No.
  • the area reduction rate is 0.
  • a solution heat treatment was performed by heating and cooling the thick plate that had been forged and rolled under the above manufacturing conditions to 110 ° C.
  • the austenitic stainless steel sheet of the present invention can be applied as a structural material of a superconducting coil for a thermonuclear fusion reactor (ITER), which is expected as a next-generation energy source.
  • ITER thermonuclear fusion reactor
  • the austenitic stainless steel sheet according to the present invention can be applied to large-sized superconducting equipment and structures for LNG (liquefied natural gas), and so on. It is expected to make a great contribution to various industrial fields.
  • LNG liquefied natural gas
  • the present invention has great industrial and social effects.
  • the present invention has great industrial applicability.

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  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)

Abstract

Plaque en acier inoxydable en austénite roulée ayant une épaisseur supérieure ou égale à 100 mm, caractérisée en ce qu'elle comprend les composants suivants (% en poids) : C : 0,08 % ou moins, N : 0,10 à 0,22 % inclus, C + N : 0,12 % ou plus, Si : 0,01 à 2,0 % inclus, Mn : 0,1 à 2,0 % inclus, Cr : 15 à 27 % inclus, Ni : 8 à 20 % inclus, Mo : 4 % ou moins, Co : 0,1 % ou moins, Cu : 0,1 à 3 % inclus, Al : 0,001 à 0,10 % inclus, et Ca : 0,0005 à 0,01 % inclus. En outre, la plaque a une teneur calculée en δ-ferrite (δ cal [vol %]) de -7 à 4 % inclus et un allongement supérieur ou égal à 30 %, à la fois dans le sens de la largeur et dans le sens de la longueur, tel que mesuré à une position arbitraire dans le sens de l'épaisseur.
PCT/JP2007/063186 2006-07-13 2007-06-25 PLAQUE EN ACIER INOXYDABLE EN AUSTÉNITE ROULÉE AYANT UNE ÉPAISSEUR SUPÉRIEURE OU ÉGALE À 100 mm ET PROCÉDÉ DE PRODUCTION DE CELLE-CI Ceased WO2008007572A1 (fr)

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EP07767966.0A EP2042616B1 (fr) 2006-07-13 2007-06-25 PLAQUE EN ACIER INOXYDABLE EN AUSTÉNITE ROULÉE AYANT UNE ÉPAISSEUR SUPÉRIEURE OU ÉGALE À 100 mm ET PROCÉDÉ DE PRODUCTION DE CELLE-CI
CN200780000850XA CN101341271B (zh) 2006-07-13 2007-06-25 厚度为100mm以上的奥氏体系不锈钢轧制钢板及其制造方法

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JP2006-192702 2006-07-13

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JP2016047554A (ja) * 2014-08-25 2016-04-07 Ｊｆｅスチール株式会社 スラブ鍛造方法
CN111373067A (zh) * 2017-12-06 2020-07-03 株式会社Posco 具有优异的耐腐蚀性的非磁性奥氏体不锈钢及其制造方法
CN113560343A (zh) * 2021-06-25 2021-10-29 鞍钢股份有限公司 一种控制低碳奥氏体不锈钢特厚板晶粒度的方法

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JP2016047554A (ja) * 2014-08-25 2016-04-07 Ｊｆｅスチール株式会社 スラブ鍛造方法
CN111373067A (zh) * 2017-12-06 2020-07-03 株式会社Posco 具有优异的耐腐蚀性的非磁性奥氏体不锈钢及其制造方法
CN113560343A (zh) * 2021-06-25 2021-10-29 鞍钢股份有限公司 一种控制低碳奥氏体不锈钢特厚板晶粒度的方法

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CN101341271A (zh) 2009-01-07
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