WO2022114145A1 - 二相ステンレス鋼板および二相ステンレス熱延板、ならびに二相ステンレス鋼板の製造方法 - Google Patents

二相ステンレス鋼板および二相ステンレス熱延板、ならびに二相ステンレス鋼板の製造方法 Download PDF

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WO2022114145A1
WO2022114145A1 PCT/JP2021/043464 JP2021043464W WO2022114145A1 WO 2022114145 A1 WO2022114145 A1 WO 2022114145A1 JP 2021043464 W JP2021043464 W JP 2021043464W WO 2022114145 A1 WO2022114145 A1 WO 2022114145A1
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stainless steel
rolling
content
phase
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French (fr)
Japanese (ja)
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拓也 櫻庭
詠一朗 石丸
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Nippon Steel Stainless Steel Corp
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Nippon Steel Stainless Steel Corp
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Priority to JP2022565463A priority Critical patent/JP7483049B2/ja
Priority to US18/039,191 priority patent/US20240002969A1/en
Priority to CN202180079295.4A priority patent/CN116490625B/zh
Priority to KR1020237017943A priority patent/KR102891296B1/ko
Priority to EP21898117.3A priority patent/EP4253587A4/en
Publication of WO2022114145A1 publication Critical patent/WO2022114145A1/ja
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • 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
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    • 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
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    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • 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
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • 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
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    • C21—METALLURGY OF IRON
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a duplex stainless steel sheet, a duplex stainless hot rolled sheet, and a method for manufacturing a duplex stainless steel sheet.
  • Stainless steel is used for various purposes as a typical corrosion-resistant material, but in recent years, it has not only been free from rusting and perforation due to corrosion, but in recent years, it has become an application that requires a beautiful appearance after construction. Is being applied.
  • Patent Document 1 Cr: 16 to 35%, Ti: 0.05 to 0.5%, Mo: 0 to 6% (including no additive), Nb: 0-1 in mass%.
  • a highly corrosion-resistant stainless steel sheet for exterior building materials which is a steel sheet and has an excellent ability to prevent the occurrence of band-shaped appearance unevenness, in which the brightness difference ⁇ L within the plate width of the steel sheet surface in a direction orthogonal to the rolling direction is adjusted to 5 or less. ing.
  • Duplex stainless steel sheets have better weather resistance than austenitic stainless steel sheets.
  • the conventional duplex stainless steel thin plate has long-period unevenness (surface waviness) in the surface roughness.
  • Duplex stainless steel sheets with surface waviness may have streaks caused by the surface waviness. Therefore, there is room for improvement in conventional duplex stainless steel when a beautiful appearance is required.
  • the present invention has been made in view of the above problems, and an object of the present invention is to provide a duplex stainless steel sheet, a duplex stainless hot-rolled sheet, and a duplex stainless steel sheet having a beautiful appearance. There is something in it.
  • the present inventors have found that when a large number of ferrite phase crystal grains having a specific crystal orientation are present in a two-phase stainless steel plate, the crystal grains are deformed, for example, mirror-polished. Found that it deforms differently from crystal grains in other orientations. Then, the present inventors have found that surface waviness occurs due to the different deformation behaviors that occur between the different crystal grains. Therefore, the present inventors have come up with the idea of suppressing surface waviness by randomizing the texture of the ferrite phase.
  • the ferrite phase is softened by annealing the hot-rolled plate at a low temperature for a long time, and strain is preferentially introduced into the softened ferrite phase to introduce a ferrite phase.
  • the two-phase stainless steel plate according to one aspect of the present invention is a two-phase stainless steel plate containing an austenite phase and a ferrite phase, in terms of mass%, C: 0.080% or less, Si: 1.00%.
  • Mn 4.00% or less
  • P 0.040% or less
  • S 0.0300% or less
  • Cr 18.00 to 28.00%
  • Mo It contains 5.00% or less
  • N 0.080 to 0.320%
  • the balance consists of Fe and impurities, which is perpendicular to the rolling direction on the rolled surface.
  • the area ratio S ⁇ 001> / S ⁇ 111> which is the ratio of the area ratio S ⁇ 001 > of the aggregate structure of the ferrite phase oriented in the ⁇ 001> direction in the rolling vertical direction, is 0.90 to 1.10. be.
  • the duplex stainless steel sheet according to the above [1] may have a surface waviness height of 0.3 ⁇ m or less in the rolling direction.
  • the duplex stainless steel sheet according to the above [1] or [2] has a mass% of C: 0.030% or less, Si: 0.75% or less, Mn: 2.00 to 4.00%. , P: 0.040% or less, S: 0.0200% or less, Ni: 1.50 to 2.50%, It contains Cr: 18.00 to 21.50%, Mo: 0.60% or less, Cu: 0.50 to 1.50%, and N: 0.150 to 0.200%, and the balance is Fe. And may consist of impurities.
  • the two-phase stainless steel plate according to any one of [1] to [3] above has Al: 0.003 to 0.050%, O: 0.
  • Nb 0.005 to 0.20%
  • Ti 0.005 to 0.20%
  • Co 0.005 to 0.25%
  • V 0.005 to 0.15%
  • Sn 0.005 to 0.20%
  • Sb 0.005 to 0.20%
  • Ga 0.001 to 0.050%
  • Zr 0.005 to 0.50%
  • Ta 0.005 to 0. It may contain one or more selected from the group consisting of 100% and B: 0.0002 to 0.0050%.
  • the two-phase stainless hot-rolled plate according to another aspect of the present invention is a two-phase stainless hot-rolled plate containing an austenite phase and a ferrite phase, in terms of mass%, C: 0.080% or less, Si. : 1.00% or less, Mn: 4.00% or less, P: 0.040% or less, S: 0.0300% or less, Ni: 1.50 to 8.00%, Cr: 18.00 to 28. It contains 00%, Mo: 5.00% or less, Cu: 0.05 to 1.50%, and N: 0.080 to 0.320%, and the balance is composed of Fe and impurities, and the austenite phase is described above.
  • the difference between the Vickers hardness of the above-mentioned ferrite phase and the Vickers hardness of the ferrite phase is 50 HV or more.
  • the two-phase stainless steel hot-rolled plate according to [5] above has Al: 0.003 to 0.050%, O: 0.0070% or less, Nb in mass%, instead of a part of Fe.
  • 0.005 to 0.20% Ti: 0.005 to 0.20%, Co: 0.005 to 0.25%, V: 0.005 to 0.15%, Sn: 0.005 to 0 .20%, Sb: 0.005 to 0.20%, Ga: 0.001 to 0.050%, Zr: 0.005 to 0.50%, Ta: 0.005 to 0.100%, and B: It may contain one or more selected from the group consisting of 0.0002 to 0.0050%.
  • the method for producing a two-phase stainless steel sheet according to still another aspect of the present invention is, in terms of mass%, C: 0.080% or less, Si: 1.00% or less, Mn: 4.00% or less, P. : 0.040% or less, S: 0.0300% or less, Ni: 1.50 to 6.80%, Cr: 18.00 to 28.00%, Mo: 5.00% or less, Cu: 0.05 Hot rolling step of hot rolling a stainless steel material containing ⁇ 1.50% and N: 0.080 ⁇ 0.320%, the balance of which is Fe and impurities, and winding at a temperature of 680 ° C or higher. A heat treatment step of holding the stainless steel material after the hot rolling step at a temperature of 500 ° C.
  • the stainless steel material is changed to a part of Fe, and the mass% is Al: 0.003 to 0.050%, O: 0.
  • Nb 0.005 to 0.20%
  • Ti 0.005 to 0.20%
  • Co 0.005 to 0.25%
  • V 0.005 to 0.15%
  • Sn 0.005 to 0.20%
  • Sb 0.005 to 0.20%
  • Ga 0.001 to 0.050%
  • Zr 0.005 to 0.50%
  • Ta 0.005 to 0 It may contain one or more selected from the group consisting of 100% and B: 0.0002 to 0.0050%.
  • the two-phase stainless steel plate according to the present embodiment is a two-phase stainless steel plate containing an austenite phase and a ferrite phase, in terms of mass%, C: 0.080% or less, Si: 1.00% or less, Mn: 4. .00% or less, P: 0.040% or less, S: 0.0300% or less, Ni: 1.50 to 8.00%, Cr: 18.00 to 28.00%, Mo: 5.00% or less , Cu: 0.05 to 1.50%, and N: 0.080 to 0.320%, the balance of which consists of Fe and impurities, which is a plate perpendicular to the rolling direction on the rolled surface.
  • the area ratio S ⁇ 001> / S ⁇ 111> which is the ratio of the area ratio S ⁇ 001 > of the aggregate structure of the ferrite phase oriented in the ⁇ 001> direction, is 0.90 to 1.10.
  • the duplex stainless steel sheet according to the present embodiment will be described in detail below.
  • the C content is set to 0.080% or less.
  • the C content is preferably 0.030% or less, more preferably 0.025% or less.
  • the lower limit of the C content is not particularly limited, but from the viewpoint of cost, the C content is preferably 0.001% or more, more preferably 0.007% or more.
  • Si acts as a deoxidizing agent and a desulfurizing agent. If the Si content exceeds 1.00%, the toughness decreases, so the Si content is set to 1.00% or less.
  • the Si content is preferably 0.65% or less.
  • the Si content is preferably 0.05% or more.
  • the Si content is more preferably 0.30% or more.
  • Mn 4.00% or less
  • Mn is a relatively inexpensive element, but it suppresses the precipitation of Cr nitrides by increasing the amount of austenite phase in the stainless steel sheet and further increasing the solid solubility of nitrogen. effective. On the other hand, excessive content causes deterioration of corrosion resistance. Therefore, the Mn content is set to 4.00% or less.
  • the Mn content is preferably 2.50% or less.
  • the Mn content is preferably 0.74% or more, more preferably 0.85% or more, and even more preferably 2.00% or more.
  • P 0.040% or less
  • P is an element that is inevitably contained in the stainless steel sheet, but the P content is 0.040% or less because it deteriorates hot workability.
  • the P content is preferably 0.035% or less.
  • the lower limit of the P content is not particularly limited, but from the viewpoint of cost, the P content is preferably 0.005% or more.
  • S 0.0300% or less
  • S is an element inevitably contained in the stainless steel sheet like P, but deteriorates hot workability, toughness, and corrosion resistance. Therefore, the S content is 0.0300% or less.
  • the S content is preferably 0.0200% or less.
  • the lower limit of the S content is not particularly limited, but from the viewpoint of cost, the S content is preferably 0.0001% or more.
  • the S content is more preferably 0.0005% or more.
  • Ni 1.50-8.00%
  • Ni is an element that improves the design of stainless steel sheets in the present invention.
  • the Ni content is too low, the solid solution Ni in the austenite phase in the hot-rolled plate is reduced and softened, so that the difference between the Vickers hardness of the austenite phase and the Vickers hardness of the ferrite phase in the hot-rolled plate described later is 50 HV or more. Not satisfied. Therefore, when the Ni content is too low, in the present invention, in the cold-worked steel sheet, the "rolling vertical direction which is the direction perpendicular to the rolling direction on the rolled surface and parallel to the plate thickness direction" described later.
  • the area ratio S ⁇ 001> / S ⁇ 111> which is the ratio of the area ratio S ⁇ 001> of the aggregate, does not satisfy 0.90 to 1.10. That is, when the Ni content is too small, the surface waviness height in the rolling direction does not become 0.3 ⁇ m or less, so that the effect of improving the designability in which the surface waviness height is controlled to be small cannot be obtained. Therefore, the Ni content is 1.50% or more.
  • the Ni content is preferably 2.00% or more. On the other hand, if the Ni content is excessive, not only the cost increases, but also the austenite phase becomes excessive and the hot workability deteriorates. Therefore, the Ni content is 8.00% or less.
  • the Ni content is preferably 6.90% or less, more preferably 6.80% or less, and even more preferably 2.50% or less.
  • Cr 18.00 to 28.00%
  • Cr is an element that improves the corrosion resistance of stainless steel sheets. From the viewpoint of corrosion resistance, the Cr content is 18.00% or more. The Cr content is preferably 20.50% or more, and more preferably 21.00% or more. On the other hand, Cr is also an element that increases the ferrite phase, and if the stainless steel sheet contains an excessive amount of Cr, the ferrite phase becomes excessive and the toughness deteriorates. Therefore, the Cr content is set to 28.00% or less. The Cr content is preferably 24.50% or less, more preferably 21.50% or less.
  • Mo 5.00% or less
  • Mo has a high corrosion resistance improving effect exceeding Cr, but it is a very expensive element, and if the Mo content is excessive, the production cost increases. Further, if the Mo content is excessive, the stainless steel sheet is hardened and the workability is deteriorated. Therefore, the Mo content is set to 5.00% or less.
  • the Mo content is preferably 3.00% or less, more preferably 2.95% or less, and even more preferably 0.60% or less. Since the effect of improving the corrosion resistance of Mo is poor when the Mo content is less than 0.01%, the Mo content is set to, for example, 0.01% or more.
  • the Mo content is preferably 0.05% or more, more preferably 0.20% or more.
  • Cu 0.05 to 1.50% Like Ni, Cu is an element that suppresses the dissolution of stainless steel sheets in a low pH environment. However, if the stainless steel sheet contains an excessive amount of Cu, the hot workability is significantly impaired, so the Cu content is set to 1.50% or less.
  • the Cu content is preferably 1.40% or less. On the other hand, the above effect cannot be obtained when the Cu content is less than 0.05%. Therefore, the Cu content is set to 0.05% or more.
  • the Cu content is preferably 0.60% or more, more preferably 0.70% or more.
  • N 0.080 to 0.320%
  • N is an element that significantly enhances corrosion resistance and increases the amount of austenite phase.
  • the N content is 0.080% or more.
  • the N content is preferably 0.150% or more, and more preferably 0.155% or more.
  • the N content exceeds 0.320%, a nitride is formed in the steel to reduce corrosion resistance and toughness, so the N content is set to 0.320% or less.
  • the N content is preferably 0.200% or less.
  • the balance other than the above-mentioned elements is Fe and impurities.
  • elements other than the above-mentioned elements can also be contained within a range that does not impair the effects of the present embodiment.
  • the impurities referred to here are components mixed with raw materials such as ore and scrap, and various factors in the manufacturing process when the two-phase stainless steel sheet according to the present invention is industrially manufactured, and are included in the present invention. It means something that is acceptable as long as it does not have an adverse effect.
  • duplex stainless steel sheet according to the embodiment of the present invention has been described above, but in the duplex stainless steel sheet according to the embodiment of the present invention, other elements described below are replaced with a part of Fe. , Can be appropriately contained. Since the following elements do not have to be contained, the lower limit of the content of these elements is 0%.
  • Al 0.003 to 0.050%
  • Al is an element having a strong deoxidizing action.
  • the Al content is preferably 0.003% or more.
  • the Al content is more preferably 0.005% or more.
  • Al tends to form a nitride together with N, and when the nitride is formed, the toughness is greatly reduced. Therefore, the Al content is preferably 0.050% or less.
  • the Al content is more preferably 0.040% or less.
  • the O content is preferably 0.0070% or less.
  • the O content is more preferably 0.0050% or less.
  • the lower limit of the O content is not particularly limited, but from the viewpoint of cost, the O content is preferably 0.0005% or more.
  • the O content may be 0.001% or more.
  • Nb 0.005 to 0.20%
  • Nb is an element that fixes C and N to prevent deterioration of corrosion resistance due to precipitation of Cr carbides and improves corrosion resistance.
  • the Nb content is preferably 0.005% or more.
  • the Nb content may be 0.01% or more.
  • the Nb content exceeds 0.20%, the ⁇ phase may be hardened due to solid solution strengthening and the workability may be lowered. Therefore, the Nb content is preferably 0.20% or less.
  • the Nb content may be 0.18% or less.
  • Ti 0.005 to 0.20%
  • Ti is an element that fixes C and N to prevent sensitization due to precipitation of Cr carbides and improves corrosion resistance.
  • the Ti content is preferably 0.005% or more.
  • the Ti content may be 0.01% or more.
  • the Ti content exceeds 0.20%, the ferrite phase may be hardened, the toughness may be lowered, and the surface roughness may be lowered due to the Ti-based precipitate. Therefore, the Ti content is preferably 0.20% or less.
  • the Ti content may be 0.18% or less.
  • Co 0.005-0.25%
  • Co suppresses the precipitation of Cr carbides and suppresses the deterioration of corrosion resistance.
  • the Co content is 0.005% or more, Co exerts the above effect, so that the Co content is preferably 0.005% or more.
  • the Co content may be 0.01% or more.
  • the Co content is preferably 0.25% or less.
  • the Co content may be 0.20% or less.
  • V 0.005 to 0.15%
  • V is a strong carbide-forming element. Therefore, when V, which easily forms carbides, is contained in a high temperature region, precipitation of Cr carbides is suppressed, and deterioration of corrosion resistance can be suppressed.
  • V content is 0.005% or more, V exerts the above effect, so the V content is preferably 0.005% or more.
  • the V content may be 0.01% or more, but a large V content causes hardening, so the V content is preferably 0.15% or less.
  • the V content may be 0.12% or less.
  • Sn and Sb are elements that improve corrosion resistance, but they are also solid solution strengthening elements for the ferrite phase. Therefore, the respective contents of Sn and Sb are preferably 0.20% or less. The respective contents of Sn and Sb are more preferably 0.10% or less. When the content of either Sn or Sb is 0.005% or more, the effect of improving the corrosion resistance is exhibited, so the content of each of Sn and Sb is preferably 0.005% or more. The respective contents of Sn and Sb are more preferably 0.030% or more.
  • Ga 0.001 to 0.050% Ga is an element that contributes to the improvement of corrosion resistance.
  • the Ga content is 0.001% or more, the effect of improving corrosion resistance is exhibited, so that the Ga content is preferably 0.001% or more.
  • the Ga content may be 0.005% or more.
  • the Ga content is preferably 0.050% or less.
  • the Ga content may be 0.040% or less.
  • Zr 0.005 to 0.50%
  • Zr is an element that contributes to the improvement of corrosion resistance.
  • the Zr content may be 0.01% or more.
  • the Zr content exceeds 0.50%, the effect is saturated. Therefore, the Zr content is preferably 0.50% or less.
  • the Zr content may be 0.40% or less.
  • Ta 0.005 to 0.100%
  • Ta is an element that improves corrosion resistance by modifying inclusions.
  • the Ta content is preferably 0.005% or more.
  • the Ta content may be 0.01% or more.
  • the Ta content is more preferably 0.050% or less.
  • B 0.0002 to 0.0050%
  • B is an element that has the effect of suppressing secondary embrittlement and deterioration of hot workability. Further, B is an element that does not affect the corrosion resistance.
  • B content is 0.0002% or more, B exerts the above effect, so that the B content is preferably 0.0002% or more.
  • the B content may be 0.0005% or more.
  • the B content is more preferably 0.0022% or less, still more preferably 0.0020% or less.
  • the duplex stainless steel sheet according to the present embodiment has the above chemical components, but has C: 0.030% or less, Si: 0.75% or less, Mn: 2.00 to 4.00%, P: 0. 040% or less, S: 0.0200% or less, Ni: 1.50 to 2.50%, Cr: 20.50 to 21.50%, Mo: 0.60% or less, Cu: 0.50 to 1. It is more preferable to contain 50% and N: 0.150 to 0.200%. When the duplex stainless steel sheet has the chemical composition, it becomes more excellent in corrosion resistance.
  • the two-phase stainless steel plate according to the present embodiment is vertical to rolling with respect to the area ratio S ⁇ 111> of the aggregate structure of the ferrite phase oriented in the ⁇ 111> direction in the rolling vertical direction at the center of the plate thickness in the cross section in the rolling vertical direction.
  • the area ratio S ⁇ 001> / S ⁇ 111> which is the ratio of the area ratio S ⁇ 001 > of the aggregate structure of the ferrite phase oriented in the ⁇ 001> direction, is 0.90 to 1.10.
  • FIG. 1 shows an example of a reverse pole diagram crystal orientation map of a ferrite phase in a rolling vertical direction obtained by SEM-EBSD (Scanning Electron Microscope-Electron Backscatter Diffraction Pattern) analysis. Is.
  • SEM-EBSD Sccanning Electron Microscope-Electron Backscatter Diffraction Pattern
  • the central portion of the plate thickness means a range of 2t / 5 to 3t / 5 in the plate thickness direction from the surface of the steel plate, where t is the plate thickness of the steel plate.
  • the crystal orientation of the measurement point is analyzed with the measurement interval set to 1 ⁇ m.
  • the target of crystal orientation measurement is performed on crystal grains having a CI value (Confidence Index) of 0.1 or more, which is an index indicating the certainty of the calculated crystal orientation.
  • the aggregate structure in which the orientation difference in the ⁇ 111> direction with respect to the rolling vertical direction is within 15 ° is defined as the aggregate structure of the ferrite phase in which the ⁇ 111> direction is oriented in the rolling vertical direction.
  • the aggregate structure in which the orientation difference in the ⁇ 001> direction with respect to the rolling vertical direction is within 15 ° is defined as the aggregate structure of the ferrite phase oriented in the ⁇ 001> direction in the rolling vertical direction.
  • the aggregate structure of the ferrite phase oriented in the ⁇ 101> direction in the rolling vertical direction and the aggregate structure of the ferrite phase oriented in the ⁇ 411> direction in the rolling vertical direction are determined.
  • IPF Inverse Pole Figure
  • the circle-equivalent diameter of the texture of the ferrite phase oriented in the ⁇ 111> direction in the rolling vertical direction and the circle-equivalent diameter of the texture of the ferrite phase oriented in the ⁇ 001> direction in the rolling vertical direction respectively.
  • Calculate the area of the aggregate structure of. The area of each texture is determined by image analysis. From the area of each texture, the total area of the aggregates of the ferrite phases oriented in the ⁇ 111> direction and the total area of the aggregates of the ferrite phases oriented in the ⁇ 001> direction are calculated.
  • the area ratio S' ⁇ 111> of the aggregate structure of the ferrite phase oriented in the ⁇ 111> direction in the direction perpendicular to the rolling direction with respect to the area of the entire field of view is calculated, and the area ratio S' ⁇ 001> / S' ⁇ 111> is calculated.
  • the area ratio S' ⁇ 001> / S' ⁇ 111> is calculated for each field of view of the acquired SEM image, and the average value thereof is defined as the area ratio S ⁇ 001> / S ⁇ 111> .
  • the particle size of the austenite phase is about several ⁇ m, and the particle size of the ferrite phase is about 10 ⁇ m. Therefore, the SEM image acquired at an observation magnification of 1000 times contains sufficient crystal grains so that the area ratio S ⁇ 001> / S ⁇ 111> can be used as a guideline for the degree of randomization of the texture. It can be said that it is projected.
  • the texture of the ferrite phase indicates that the ⁇ 111> direction is strongly oriented in the rolling vertical direction.
  • the area ratio S ⁇ 001> / S ⁇ 111> is more than 1.10, it means that the aggregate structure of the ferrite phase is strongly oriented in the ⁇ 001> direction in the vertical direction of rolling.
  • the steel plate which is an aggregate structure of ferrite phases oriented in the ⁇ 111> direction in the TD (rolling vertical direction) or an aggregate structure of ferrite phases oriented in the ⁇ 001> direction in the TD (rolling vertical direction)
  • these crystal grains behaves differently from other aggregates.
  • the area ratio S ⁇ 001> / S ⁇ 111> is 0.90 to 1.10.
  • the area ratio S ⁇ 001> / S ⁇ 111> may be 0.92 or more, or 1.00 or more. Further, the area ratio S ⁇ 001> / S ⁇ 111> may be 1.00 or less, or 1.08 or less.
  • the duplex stainless steel sheet according to the present embodiment preferably has a surface waviness height R in the rolling direction of 0.3 ⁇ m or less.
  • the surface waviness height R in the rolling direction will be described with reference to FIG. 2.
  • FIG. 2 is a graph showing an example of a roughness curve for explaining a method of measuring the surface waviness height.
  • the surface waviness height R in the rolling direction is calculated in accordance with JIS B 0601: 2013 with a measurement interval of 0.02 mm for a length of 10 mm in the rolling direction using a surface roughness measuring machine.
  • the surface swell height R corresponds to the maximum height swell Wz described in JIS B 0601: 2013.
  • the measurement position of the surface waviness height R in the rolling direction is the center position of the plate.
  • the surface waviness height R in the rolling direction is preferably 0.3 ⁇ m or less. More preferably, the surface waviness height R in the rolling direction of the stainless steel sheet to which tensile stress is applied and a strain of 16% is applied is preferably 1.8 ⁇ m or less. If the surface waviness height R in the rolling direction of a stainless steel sheet to which tensile stress is applied and a strain of 16% is applied is 1.8 ⁇ m or less, streaks will appear even when the stainless steel sheet is processed for actual use. It becomes even more difficult to see.
  • the duplex stainless steel sheet according to the present invention is manufactured by cold rolling a stainless hot-rolled sheet manufactured by a predetermined treatment.
  • the upper limit of ⁇ HV is not particularly limited.
  • ⁇ HV may be, for example, 65 HV or less, 70 HV or less, or 75 HV or less.
  • the Vickers hardness HV ⁇ of the austenite phase and the Vickers hardness HV ⁇ of the ferrite phase are measured with a load of 0.01 kgf in accordance with JIS Z 2244: 2009. Five points are measured for each of the austenite phase and the ferrite phase at the center of the plate thickness, and the average value of each is used as a representative value.
  • ⁇ HV is 50 HV or more
  • strain is preferentially introduced into the ferrite phase in a subsequent step, for example, a cold rolling step, a temper rolling step, a processing step for actual use, or the like.
  • the area ratio S ⁇ 001> / S ⁇ 111> of the stainless steel sheet is 0.90 to 1.10.
  • ⁇ HV is 65 or more
  • the hardness difference between the austenite phase and the ferrite phase of the hot-rolled plate is large, so that the particle size of the soft phase is subdivided during cold rolling.
  • the difference in the deformability of the crystal orientation becomes less likely to occur, and even when the stainless steel plate is processed for actual use, the streak pattern becomes more difficult to be visually recognized.
  • the thickness of the duplex stainless steel sheet according to this embodiment is, for example, 0.30 mm or more and 2.00 mm or less.
  • the thickness of the duplex stainless steel sheet may be 0.50 mm or more, or 0.80 mm or more. Further, the thickness of the duplex stainless steel sheet may be 1.80 mm or less, or 1.50 mm or less. Within such a range, the effect of suppressing the streak pattern can be obtained more remarkably, and a duplex stainless steel sheet having a beautiful appearance can be obtained.
  • the method for manufacturing a two-phase stainless steel plate according to the present embodiment includes a hot rolling step of hot rolling a stainless material having the above chemical components and winding it at a temperature of 680 ° C. or higher, and a stainless steel after the hot rolling step. It has a heat treatment step of holding the material at a temperature of 500 ° C. or higher and lower than 600 ° C. for 1 hour or longer, and a cold rolling step after the heat treatment step.
  • the two-phase stainless steel plate according to the present embodiment is, for example, a steelmaking process, a hot rolling process, a heat treatment process, a hot rolling plate pickling step, a cold rolling process, a cold rolling heat treatment step, and a cold rolling plate pickling step. It is manufactured by carrying out the steps in order.
  • the production conditions are not particularly limited for the steps other than the hot rolling step and the heat treatment step, and a known method can be applied.
  • the hot rolling process, the heat treatment process, and the cold rolling process will be described below.
  • the stainless steel material having the above-mentioned chemical composition is hot-rolled and wound at a temperature of 680 ° C. or higher.
  • the stainless steel material to be subjected to hot rolling for example, stainless steel pieces obtained by continuous casting may be used.
  • the stainless steel material it is preferable to heat the stainless steel material to 1150 to 1250 ° C. before hot rolling. If the heating temperature is less than 1150 ° C., ear cracks may occur during hot rolling. On the other hand, if the heating temperature exceeds 1250 ° C., the steel pieces may be deformed in the heating furnace or scratches may easily occur during hot rolling.
  • the stainless steel material is hot-rolled.
  • the reduction rate is preferably 50% or less. If the rolling reduction ratio is larger than 50%, the difference in the structure shape in each rolling direction is promoted, and uniform fracture surface properties may not be obtained regardless of the rolling direction.
  • Hot rolling may be performed in multiple passes, and if multiple passes are performed, the rolling reduction rate per pass shall be 50% or less.
  • the winding temperature of the stainless steel material after rolling is 680 ° C or higher.
  • the ferrite phase recovers and recrystallizes first.
  • the winding temperature is set to 680 ° C. or higher.
  • the winding temperature is preferably 700 ° C. or higher.
  • the winding temperature is preferably 750 ° C. or lower.
  • Heat treatment process In this step, a heat treatment is performed in which the stainless steel material after the hot rolling step is held at a temperature of 500 ° C. or higher and lower than 600 ° C. for 1 hour or longer.
  • the heat treatment temperature is 500 ° C or higher and lower than 600 ° C. If the heat treatment temperature is less than 500 ° C., the ferrite phase is not sufficiently recovered and recrystallized, and the ferrite phase is not softened. When the ferrite phase is not softened, strain is not preferentially introduced into the ferrite phase in the cold rolling step of the subsequent step, and the ferrite phase has an orientation in which the crystal orientation is not randomized. Therefore, the heat treatment temperature is 500 ° C. or higher. The heat treatment temperature is preferably 550 ° C. or higher. On the other hand, when the heat treatment temperature is 600 ° C. or higher, the austenite phase is also softened, and the ferrite phase has an orientation in which the crystal orientation is not randomized. Therefore, the heat treatment temperature is set to less than 600 ° C. It is preferably 585 ° C. or lower.
  • the heat treatment time is 1 hour or more. If the heat treatment time is less than 1 hour, the ferrite phase is not sufficiently recovered and recrystallized, and the ferrite phase is not softened. When the ferrite phase is not softened, strain is not preferentially introduced into the ferrite phase in the cold rolling step of the subsequent step, and the ferrite phase has an orientation in which the crystal orientation is not randomized. Therefore, the heat treatment time is set to 1 hour or more.
  • the upper limit of the heat treatment time is not particularly limited. However, from the viewpoint of grain coarsening, the heat treatment time is preferably 2 hours or less.
  • the stainless steel material (hot rolled plate according to the present embodiment) after the heat treatment step is cold-rolled.
  • the cold rolling conditions are not particularly limited and may be known conditions.
  • cold rolling may be one pass or a plurality of passes.
  • the cumulative cold rolling reduction rate can be 30 to 80%, and the cold rolling temperature can be, for example, room temperature or higher and 200 ° C. or lower.
  • the stainless steel material to be cold-rolled may be a stainless steel material that has been pickled after the heat treatment process.
  • the cold rolling process introduces a large amount of rolling strain into the ferrite phase softened by the heat treatment process. As a result, crystal grains having various crystal orientations of the ferrite phase are generated, and the aggregate structure of the ferrite phase is randomized. As a result, waviness is suppressed on the surface of the steel sheet, and the generation of streaks on the surface of the steel sheet is suppressed.
  • the method for manufacturing a duplex stainless steel sheet according to the present embodiment has been described above.
  • the ⁇ 001> direction is oriented in the vertical direction of rolling with respect to the area ratio S ⁇ 111> of the aggregate structure of the ferrite phase oriented in the vertical direction of rolling.
  • a two-phase stainless steel plate having an area ratio S ⁇ 001> / S ⁇ 111> which is a ratio of the area ratio S ⁇ 001 > of the aggregate structure of the ferrite phase, is 0.90 to 1.10 is manufactured.
  • the texture of the ferrite phase of the duplex stainless steel sheet according to the present embodiment is random, the surface waviness height of the duplex stainless steel sheet in the rolling direction is suppressed. As a result, it is possible to suppress the generation of visible streaks.
  • the stainless steel material having the chemical composition shown in Table 1 was hot-rolled at a rolling reduction of 70%, and the rolled stainless steel material was wound up at the winding temperature shown in Table 2.
  • a heat treatment step was carried out at the heat treatment temperature and heat treatment time shown in Table 2 to manufacture a hot-rolled plate.
  • each of the manufactured hot-rolled plates was cold-rolled at a rolling reduction of 80% at room temperature to produce a stainless steel sheet.
  • "-" in Table 1 indicates that it was not intentionally added.
  • the Vickers hardness HV ⁇ of the austenite phase and the Vickers hardness HV ⁇ of the ferrite phase of the manufactured hot-rolled plate were measured with a load of 0.01 kgf in accordance with JIS Z 2244: 2009. Five points were measured for each of the austenite phase and the ferrite phase at the center of the plate thickness, and the average value of each was used as a representative value.
  • the area ratio S ⁇ 001> / S ⁇ 111> which is the ratio of the area ratio S ⁇ 001 > of the aggregated structure of the ferrite phase oriented in the ⁇ 001> direction, was calculated by the following method.
  • three SEM images were acquired with an observation magnification of 1000 times, and the crystal orientation of the measurement points was analyzed for each SEM image with a measurement interval of 1 ⁇ m.
  • each aggregate is calculated from the equivalent circle diameter of the aggregate of ferrite phases oriented in the ⁇ 111> direction in the vertical direction of rolling and the equivalent circle diameter of the aggregate of ferrite phases oriented in the ⁇ 001> direction in the vertical direction of rolling. did.
  • the area is calculated from the calculated equivalent circle diameter, and the total area of the texture of the ferrite phase oriented in the ⁇ 111> direction in the rolling vertical direction and the ferrite oriented in the ⁇ 001> direction in the rolling vertical direction.
  • the total area of the aggregated structure of the phases was calculated.
  • the area ratio S' ⁇ 001> of the texture of the ferrite phase oriented in the 001> direction was calculated, and the area ratio S' ⁇ 001> / S' ⁇ 111> was calculated.
  • the area ratio S' ⁇ 001> / S' ⁇ 111> was calculated for each field of view of the acquired SEM image, and the average value thereof was taken as the area ratio S ⁇ 001> / S ⁇ 111> .
  • the surface waviness height R in the rolling direction of the produced duplex stainless steel was measured by the following method.
  • the measurement interval is 0.02 mm for the length of 10 mm in the rolling vertical direction at the center position of the two-phase stainless steel plate.
  • the roughness curve of the surface of the stainless steel plate was obtained, and the surface waviness height R in the rolling direction was measured.
  • the surface waviness height R in the rolling direction was measured at the center position of the steel sheet.
  • the appearance was evaluated by visual observation. Specifically, the surface of the manufactured stainless steel sheet and the surface of the stainless steel sheet after being overhanged by a cylindrical punch are mirror-polished by simulating an example of actual use processing, and various mirror-polished surfaces are obtained. Observing from the direction, the presence or absence of streaks was confirmed. When no streaks were observed on the stainless steel sheet after the above processing, the appearance was evaluated to be extremely good (A), and streaks were observed on the stainless steel sheet before applying 16% strain. If not, the appearance was evaluated as good (B), and when a streak pattern was observed on the stainless steel sheet before applying the strain of 16%, the appearance was evaluated as poor (C). Table 2 shows the evaluation results.
  • the surface waviness height in the rolling direction of the stainless steel sheet after being applied is shown.
  • the underlined values in Table 2 indicate that they are outside the scope of the present invention.
  • the chemical composition of each of the obtained steel sheets was substantially the same as the chemical composition of each stainless steel material. Moreover, when the obtained hot-rolled plate and the stainless steel plate were observed by SEM, all the steel plates were duplex stainless steel plates.
  • the heat produced under the conditions that the winding temperature of the hot rolling process is 680 ° C. or higher, the heat treatment temperature of the heat treatment step is 500 or more and less than 600 ° C., and the heat treatment time is 1 hour or more.
  • the rolled plate had a ⁇ HV of 50 or more.
  • the stainless steel plate obtained by cold-rolling a hot-rolled plate having a ⁇ HV of 50 or more (referred to as “cold-rolled plate” in Table 2) has an area ratio of S ⁇ 001> / S ⁇ 111> . , 0.90 to 1.10.
  • the appearance evaluation results of the duplex stainless steel sheets having an area ratio S ⁇ 001> / S ⁇ 111> of 0.90 to 1,10 were good.

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PCT/JP2021/043464 2020-11-30 2021-11-26 二相ステンレス鋼板および二相ステンレス熱延板、ならびに二相ステンレス鋼板の製造方法 Ceased WO2022114145A1 (ja)

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