US20240002969A1 - Dual phase stainless steel sheet and dual phase stainless hot-rolled sheet, and method for manufacturing dual phase stainless steel sheet - Google Patents

Dual phase stainless steel sheet and dual phase stainless hot-rolled sheet, and method for manufacturing dual phase stainless steel sheet Download PDF

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US20240002969A1
US20240002969A1 US18/039,191 US202118039191A US2024002969A1 US 20240002969 A1 US20240002969 A1 US 20240002969A1 US 202118039191 A US202118039191 A US 202118039191A US 2024002969 A1 US2024002969 A1 US 2024002969A1
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stainless steel
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steel sheet
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Takuya SAKURABA
Eiichiro Ishimaru
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Nippon Steel Stainless Steel Corp
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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
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    • 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
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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
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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
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    • 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
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    • 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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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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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
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    • 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
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    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • C—CHEMISTRY; METALLURGY
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a dual phase stainless steel sheet and a dual phase stainless hot-rolled plate, and a method for manufacturing a dual phase stainless steel sheet.
  • Priority is claimed on Japanese Patent Application No. 2020-198585, filed Nov. 30, 2020, the content of which is incorporated herein by reference.
  • Stainless steel is used as a representative corrosion-resistant material in various applications, and is used not only to simply prevent rusting and hole opening due to corrosion, but in recent years, has also been used in applications that require a favorable appearance after construction.
  • Patent Document 1 discloses a highly corrosion-resistant stainless steel sheet for an exterior building material having excellent ability to prevent the occurrence of a belt-like undulated appearance, which is a bright annealed steel sheet or annealed and pickled steel sheet of a dual phase stainless steel containing in mass %, Cr: 16 to 35%, Ti: 0.05 to 0.5%, Mo: 0 to 6% (including none added), Nb: 0 to 1.0% (including none added), and N: 0.005 to 0.025%, and with a C content that is limited to 0.015% or less, and in which the brightness difference ⁇ L within the plate width on the surface of the steel sheet in a direction perpendicular to the rolling direction is adjusted to 5 or less.
  • Dual phase stainless steel sheets have better weather resistance than austenite-based stainless steel sheets.
  • conventional dual phase stainless steel thin sheets have long-term undulation (surface waviness) regarding the surface roughness.
  • surface waviness stripe patterns caused by the surface waviness may be visible. Therefore, when a favorable appearance is required, conventional dual phase stainless steels have room for improvement.
  • the present invention has been made in view of the above circumstances, and an object of the present invention is to provide a dual phase stainless steel sheet and dual phase stainless hot-rolled sheet which have a favorable appearance, and a method for manufacturing a dual phase stainless steel sheet.
  • the inventors found that, when a dual phase stainless steel sheet contains a large number of ferrite crystal grains having a specific crystal orientation, if the dual phase stainless steel sheet is deformed, for example, if mirror polishing is performed, the crystal grains deform differently from crystal grains with other orientations. Accordingly, the inventors found that surface waviness occurs due to different deformation behaviors occurring between different crystal grains. Therefore, the inventors found that the surface waviness is reduced by making the texture of the ferrite random.
  • the gist of the present invention completed based on the above findings is as follows.
  • a dual phase stainless steel sheet is a dual phase stainless steel sheet containing an austenite and a ferrite, in which the dual phase stainless steel sheet includes: in 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%, with the remainder of Fe and impurities, in which, in a center part in a sheet thickness of a cross section in a perpendicular-to-rolling direction which is a direction perpendicular to a rolling direction on a rolled surface and a direction parallel to a sheet thickness direction, an area ratio S ⁇ 001> /S ⁇ 111> which is a ratio of an area proportion S ⁇ 001> of a texture of a ferrite with the dual phase stainless steel sheet includes: in mass %
  • the dual phase stainless steel sheet according to [1], in which the surface waviness height in the rolling direction may be 0.3 ⁇ m or less.
  • the dual phase stainless steel sheet according to [1] or [2] may include, in mass %, 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: 18.00 to 21.50%, Mo: 0.60% or less, Cu: 0.50 to 1.50%, and N: 0.150 to 0.200%, with the remainder of Fe and impurities.
  • the dual phase stainless steel sheet according to any one of [1] to [3] may include, in mass %, in place of some Fe, one or more selected from the group consisting of Al: 0.003 to 0.050%, O: 0.0070% or less, 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 0.100%, and B: 0.0002 to 0.0050%.
  • a dual phase stainless hot-rolled sheet is a dual phase stainless hot-rolled sheet containing an austenite and a ferrite, in which the dual phase stainless hot-rolled sheet includes, in 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% with the remainder of Fe and impurities, in which the difference between the Vickers hardness of the austenite and the Vickers hardness of the ferrite is 50 HV or more.
  • the dual phase stainless hot-rolled sheet according to [5] may include, in mass %, in place of some Fe, one or more selected from the group consisting of Al: 0.003 to 0.050%, O: 0.0070% or less, 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 0.100%, and B: 0.0002 to 0.0050%.
  • a method for manufacturing a dual phase stainless steel sheet includes a hot rolling process in which a stainless steel containing, in 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 to 1.50% and N: 0.080 to 0.320% with the remainder of Fe and impurities is hot-rolled and coiled at a temperature of 680° C. or higher; a heat treatment process in which the stainless steel after the hot rolling process is heated at a temperature of 500° C. or higher and lower than 600° C.
  • the stainless steel may contain, in mass %, in place of some Fe, one or more selected from the group consisting of Al: 0.003 to 0.050%, O: 0.0070% or less, 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 0.100%, and B: 0.0002 to 0.0050%.
  • FIG. 1 is a diagram showing an example of an inverse pole figure crystal orientation map of a ferrite in a perpendicular-to-rolling direction (transverse direction: TD) obtained by SEM-EBSD analysis.
  • FIG. 2 is a graph showing an example of a roughness curve for illustrating a method of measuring a surface waviness height.
  • a dual phase stainless steel sheet is a dual phase stainless steel sheet containing an austenite and a ferrite, including: in 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%, with the remainder of Fe and impurities, in which, in a center part in a sheet thickness of a cross section in a perpendicular-to-rolling direction (TD) which is a direction perpendicular to a rolling direction on a rolled surface and a direction parallel to a sheet thickness direction, an area ratio S ⁇ 001> /S ⁇ 111> which is a ratio of the area proportion S ⁇ 001> of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-
  • TD
  • % indicating a component means mass %.
  • the C content exceeds 0.080%, corrosion resistance decreases due to Cr carbide precipitation. Therefore, a small C content is desirable, and up to 0.080% or less is acceptable. Therefore, the C content is 0.080% or less.
  • the C content is preferably 0.030% or less and more preferably 0.025% or less.
  • the lower limit of the C content is not particularly limited, and in consideration of cost, the C content is preferably 0.001% or more and more preferably 0.007% or more.
  • Si acts as a deoxidizing agent or a desulfurizing agent.
  • the Si content exceeds 1.00%, since the toughness deteriorates, 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 is a relatively inexpensive element, it has an effect of minimizing Cr nitride precipitation by increasing the amount of the austenite in the stainless steel sheet and additionally increasing the solid solubility of nitrogen. On the other hand, an excessive content thereof causes deterioration of corrosion resistance. Therefore, the Mn content is 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 still more preferably 2.00% or more.
  • the P is an element that is inevitably contained in a stainless steel sheet, but since it deteriorates hot workability, the P content is set to 0.040% or less.
  • the P content is preferably 0.035% or less.
  • the lower limit of the P content is not particularly limited, and in consideration of cost, the P content is preferably 0.005% or more.
  • 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, and in consideration of cost, the S content is preferably 0.0001% or more.
  • the S content is more preferably 0.0005% or more.
  • Ni is an element that improves design properties of a stainless steel sheet in the present invention.
  • the Ni content is too small, since the solid solution of Ni in the austenite in the hot-rolled sheet is reduced and softened, the difference between the Vickers hardness of the austenite and the Vickers hardness of the ferrite in the hot-rolled sheet to be described below of 50 HV or more is not satisfied.
  • an area ratio S ⁇ 001> /S ⁇ 111> which is a ratio of the area proportion S ⁇ 001> of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction to the area proportion S ⁇ 111> of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction being 0.90 to 1.10” is not satisfied.
  • the Ni content is 1.50% or more.
  • the Ni content is preferably 2.00% or more.
  • the Ni content is 8.00% or less.
  • the Ni content is preferably 6.90% or less, more preferably 6.80% or less, and still more preferably 2.50% or less.
  • Cr is an element that improves corrosion resistance of a stainless steel sheet. In consideration 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 an element that increases the ferrite content, and when the stainless steel sheet contains an excessive amount of Cr, the amount of ferrite becomes excessive, and the toughness deteriorates. Therefore, the Cr content is 28.00% or less. The Cr content is preferably 24.50% or less and more preferably 21.50% or less.
  • the Mo content is 5.00% or less.
  • the Mo content is preferably 3.00% or less, more preferably 2.95% or less, and still more preferably 0.60% or less.
  • the Mo content is thus, for example, 0.01% or more.
  • the Mo content is preferably 0.05% or more and more preferably 0.20% or more.
  • Cu is an element that minimizes dissolution of a stainless steel sheet in a low pH environment.
  • the Cu content is 1.50% or less.
  • the Cu content is preferably 1.40% or less.
  • the above effect cannot be obtained when the Cu content is less than 0.05%. Therefore, the Cu content is 0.05% or more.
  • the Cu content is preferably 0.60% or more and more preferably 0.70% or more.
  • N is an element that significantly increases corrosion resistance and increases the amount of the austenite.
  • 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 is 0.320% or less.
  • the N content is preferably 0.200% or less.
  • the remainder other than the above elements is composed of Fe and impurities.
  • elements other than the above elements can be contained within a range in which the effects of the present embodiment are not impaired.
  • impurities refers to components that are mixed in from raw materials such as ore and scrap and due to various factors in the manufacturing process when the dual phase stainless steel sheet according to the present invention is industrially manufactured, but these are allowable as long as they do not adversely influence the present invention.
  • Al is an element having a strong deacidifying action.
  • the Al content is preferably 0.003% or more for the deacidifying action of Al.
  • the Al content is more preferably 0.005% or more.
  • Al easily forms nitrides together with N, and when nitrides are formed, the toughness greatly deteriorates. 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, and in consideration of cost, the O content is preferably 0.0005% or more.
  • the O content may be 0.001% or more.
  • Nb is an element that fixes C and N, prevents a decrease in corrosion resistance due to Cr carbide precipitation 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%, since the a phase may harden due to solid solution strengthening and the workability may deteriorate, the Nb content is preferably 0.20% or less.
  • the Nb content may be 0.18% or less.
  • Ti is an element that fixes C and N, prevents sensitization due to Cr carbide precipitation, 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 is hardened, the toughness is lowered, and additionally, the surface roughness may decrease due to Ti-based precipitates. Therefore, the Ti content is preferably or less.
  • the Ti content may be 0.18% or less.
  • Co reduces Cr carbide precipitation and reduces a decrease in corrosion resistance.
  • the Co content is preferably 0.005% or more.
  • the Co content may be 0.01% or more.
  • the Co content is preferably or less.
  • the Co content may be 0.20% or less.
  • V is a strong carbide forming element. Therefore, when V, which easily forms carbides in a high-temperature range, is contained, Cr carbide precipitation can be reduced and a decrease in corrosion resistance can be reduced.
  • the V content is or more, since V exhibits the above effect, the V content is preferably 0.005% or more.
  • the V content may be 0.01% or more.
  • the V content is preferably 0.15% or less.
  • the V content may be 0.12% or less.
  • each amount of Sn and Sb is preferably 0.20% or less. Each amount of Sn and Sb is more preferably 0.10% or less. When the amount of either Sn or Sb is 0.005% or more, since the effect of improving corrosion resistance is exhibited, each amount of Sn and Sb is preferably 0.005% or more. Each amount of Sn and Sb is more preferably 0.030% or more.
  • Ga 0.001 to 0.050%
  • Ga is an element that contributes to improving corrosion resistance.
  • 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 is an element that contributes to improving corrosion resistance.
  • the Zr content is preferably 0.005% or more.
  • the Zr content may be 0.01% or more.
  • the Zr content exceeds 0.50%, the effect reaches saturation. 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 preferably 0.100% or less.
  • the Ta content is more preferably 0.050% or less.
  • B is an element that exhibits an effect of reducing secondary processing embrittlement and deterioration of hot workability.
  • B is an element that does not influence corrosion resistance.
  • the B content is preferably 0.0002% or more.
  • the B content may be 0.0005% or more.
  • the B content is preferably 0.0050% or less.
  • the B content is more preferably 0.0022% or less, and even more preferably 0.0020% or less.
  • the dual phase stainless steel sheet according to the present embodiment has the above chemical components, but preferably contains 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 1.50%, and N: 0.150 to 0.200%.
  • the dual phase stainless steel sheet has the chemical components, it has better corrosion resistance.
  • an area ratio S ⁇ 001> /S ⁇ 111> which is a ratio of the area proportion S ⁇ 001> of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction to the area proportion S ⁇ 111> of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction is 0.90 to 1.10.
  • FIG. 1 is a diagram showing an example of an inverse pole figure crystal orientation map of the ferrite in the perpendicular-to-rolling direction obtained by Scanning Electron Microscope-Electron Back Scatter Diffraction Pattern (SEM-EBSD) analysis.
  • SEM-EBSD Scanning Electron Microscope-Electron Back Scatter Diffraction Pattern
  • the center part in the sheet thickness of the cross section in the perpendicular-to-rolling direction obtained by cutting at the position of the center of the sheet width 3 or more fields of view of SEM images are acquired at an observation magnification of 1,000.
  • the center part in the sheet thickness refers to a range of 2t/5 to 3t/5 in the sheet thickness direction from the surface of the steel sheet when the sheet thickness of the steel sheet is t.
  • the crystal orientation of the measurement point is analyzed with a measurement interval of 1 ⁇ m.
  • a crystal orientation measurement target is a crystal grain having a CI value (Confidence Index) of 0.1 or more, which is an index indicating the likelihood of the calculated crystal orientation.
  • a texture in which the orientation difference in the ⁇ 111> direction with respect to the perpendicular-to-rolling direction is within 15° is defined as a texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction.
  • a texture in which the orientation difference in the ⁇ 001> direction with respect to the perpendicular-to-rolling direction is within 15° is defined as a texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction.
  • the texture of the ferrite with the ⁇ 101> direction oriented in the perpendicular-to-rolling direction and the texture of the ferrite with the ⁇ 411> direction oriented in the perpendicular-to-rolling direction are defined. Therefore, for example, an inverse pole figure crystal orientation map (Inverse Pole Figure (IPF) map) shown in FIG. 1 is obtained.
  • IPF Inverse Pole Figure
  • the area of each texture is calculated from the equivalent circle diameter of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction and the equivalent circle diameter of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction.
  • the area of each texture is subjected to image analysis. From the area of each texture, the total area of the texture of the ferrite with the oriented ⁇ 111> direction and the total area of the texture of the ferrite with the oriented ⁇ 001> direction are calculated.
  • the area proportion S′ ⁇ 111> of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction and the area proportion S′ ⁇ 001> of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction with respect to the area of one entire field of view are 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 grain size of the austenite is about several ⁇ m, and the grain size of the ferrite is about 10 ⁇ m. Therefore, in the SEM image acquired at an observation magnification of 1,000, it can be said that sufficient crystal grains are projected so that the area ratio S ⁇ 001> /S ⁇ 111> can be used as an index of the degree of randomization of the texture.
  • the texture of the ferrite indicates that the ⁇ 111> direction is strongly oriented in the perpendicular-to-rolling direction.
  • the texture of the ferrite indicates that the ⁇ 001> direction is strongly oriented in the perpendicular-to-rolling direction.
  • 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.
  • the area ratio S ⁇ 001> /S ⁇ 111> may be 1.00 or less or 1.08 or less.
  • the dual phase stainless steel sheet according to the present embodiment preferably has a surface waviness height R of 0.3 ⁇ m or less in the rolling direction.
  • the surface waviness height R in the rolling direction will be described.
  • FIG. 2 is a graph showing an example of a roughness curve for illustrating a method of measuring the surface waviness height.
  • the surface waviness height R in the rolling direction is calculated according to JIS B 0601: 2013 using a surface roughness measuring machine at a measurement interval of 0.02 mm for a length of 10 mm in the rolling direction.
  • the surface waviness height R corresponds to the maximum height waviness 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 sheet.
  • 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 a tensile stress is applied and a strain of 16% is applied is preferably 1.8 ⁇ m or less. When the surface waviness height R in the rolling direction of the stainless steel sheet to which a tensile stress is applied and a strain of 16% is applied is 1.8 lam or less, even if a stainless steel sheet is processed for actual use, stripe patterns become even less visible.
  • the dual phase stainless steel sheet according to the present invention is manufactured by performing cold rolling on the stainless hot-rolled sheet manufactured according to 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 and the Vickers hardness HV ⁇ of the ferrite are measured under a load of 0.01 kgf according to JIS Z 2244: 2009. The austenite and the ferrite are each measured at five points at the center part in the sheet thickness, and an average value thereof is used as a representative value.
  • ⁇ HV is 50 HV or more
  • a strain is preferentially introduced into the ferrite in subsequent processes, for example, a cold rolling process, a temper rolling process or a processing process for actual use.
  • the area ratio S ⁇ 001> /S ⁇ 111> of the stainless steel sheet becomes 0.90 to 1.10.
  • waviness is reduced on the surface of the steel sheet, and the occurrence of stripe patterns on the surface of the steel sheet is reduced.
  • ⁇ HV is 65 or more, since the hardness difference between the austenite and the ferrite of the hot-rolled sheet is large, the grain size of the soft phase is subdivided during cold rolling. Thereby, the difference in deformability of the crystal orientation is less likely to occur, and even if a stainless steel sheet is processed for actual use, stripe patterns become even less visible.
  • the sheet thickness of the dual phase stainless steel sheet according to the present embodiment is, for example, 0.30 mm or more and 2.00 mm or less.
  • the sheet thickness of the dual phase stainless steel sheet may be 0.50 mm or more or 0.80 mm or more.
  • the sheet thickness of the dual phase stainless steel sheet may be 1.80 mm or less or 1.50 mm or less. Within such a range, a more remarkable effect of reducing stripe patterns can be obtained, and a dual phase stainless steel sheet having a favorable appearance can be obtained.
  • the method for manufacturing a dual phase stainless steel sheet according to the present embodiment includes a hot rolling process in which a stainless steel having the above chemical components is subjected to hot rolling and coiled at a temperature of 680° C. or higher, a heat treatment process in which the stainless steel after the hot rolling process is heated at a temperature of 500° C. or higher and lower than 600° C. and maintained for 1 hour or longer, and a cold rolling process after the heat treatment process.
  • the dual phase stainless steel sheet according to the present embodiment is manufactured by performing, for example, a steelmaking process, the hot rolling process, the heat treatment process, a hot-rolled sheet pickling process, the cold rolling process, a heat treatment process after cold rolling, and a cold-rolled sheet pickling process, in this order.
  • manufacturing conditions are not particularly limited, and known methods can be applied.
  • the hot rolling process, the heat treatment process and the cold rolling process will be described.
  • a stainless steel having the above chemical components is subjected to hot rolling and coiled at a temperature of 680° C. or higher.
  • a stainless steel piece obtained by continuous casting may be used as the stainless steel to be hot-rolled.
  • the stainless steel it is preferable to heat the stainless steel to 1,150 to 1,250° C. before hot rolling.
  • the heating temperature is lower than 1,150° C., ear cracking may occur during hot rolling.
  • the heating temperature exceeds 1,250° C., a steel piece may be deformed in a heating furnace or scratches may easily occur during hot rolling.
  • the reduction rate is preferably 50% or less. When the reduction rate is more than 50%, the difference in the structure shape for each rolling direction is promoted, and regardless of the rolling direction, uniform fracture surface properties may not be obtained.
  • Hot rolling may be performed over a plurality of passes, and when a plurality of passes are performed, the reduction rate per pass is 50% or less.
  • the coiling temperature of the stainless steel after rolling is 680° C. or higher. Between the ferrite and the austenite, recovery and recrystallization of the ferrite occur first. When the coiling temperature of the stainless steel increases, recovery of the ferrite during coiling occurs, and recrystallization occurs in a part of the ferrite. When the coiling temperature is lower than 680° C., the ferrite is not sufficiently recovered during coiling. Therefore, the coiling temperature is 680° C. or higher.
  • the coiling temperature is preferably 700° C. or higher.
  • the coiling temperature is preferably 750° C. or lower. When the coiling temperature is 750° C. or lower, it is possible to further reduce recovery and recrystallization of the austenite.
  • the stainless steel after the hot rolling process is heated at a temperature of 500° C. or higher and lower than 600° C. and maintained for 1 hour or longer.
  • the heat treatment temperature is 500° C. or higher and lower than 600° C.
  • the heat treatment temperature is lower than 500° C.
  • recovery and recrystallization of the ferrite are insufficient, and the ferrite is not softened.
  • the heat treatment temperature is 500° C. or higher.
  • the heat treatment temperature is preferably 550° C. or higher.
  • the heat treatment temperature is lower than 600° C., and preferably 585° C. or lower.
  • the heat treatment time is 1 hour or longer.
  • the heat treatment time is shorter than 1 hour, recovery and recrystallization of the ferrite are insufficient, and the ferrite is not softened.
  • the heat treatment time is 1 hour or longer.
  • the upper limit of the heat treatment time is not particularly limited. However, in consideration of crystal grain coarsening, the heat treatment time is preferably 2 hours or shorter.
  • the stainless steel after the heat treatment process (hot-rolled sheet according to the present embodiment) is subjected to cold rolling.
  • Cold rolling conditions are not particularly limited and known conditions may be used.
  • cold rolling may be performed in one pass or a plurality of passes.
  • the cumulative cold rolling reduction rate may be 30 to 80%, and the cold rolling temperature may be, for example, room temperature or higher and 200° C. or lower.
  • the stainless steel to be cold-rolled may be a stainless steel that has been pickled after the heat treatment process.
  • a dual phase stainless steel sheet is manufactured in which, in a center part in the sheet thickness of the cross section in the perpendicular-to-rolling direction, an area ratio S ⁇ 001> /S ⁇ 111> which is a ratio of the area proportion S ⁇ 001> of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction to the area proportion S ⁇ 111> of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction is 0.90 to 1.10. Since the dual phase stainless steel sheet according to the present embodiment has a random texture of the ferrite, the surface waviness height in the rolling direction of the dual phase stainless steel sheet is reduced. As a result, it is possible to reduce the occurrence of visible stripe patterns.
  • Stainless steels having the chemical components shown in Table 1 were hot-rolled at a reduction rate of 70% and the rolled stainless steels were coiled at a coiling temperature shown in Table 2.
  • the heat treatment process was performed at a heat treatment temperature and for a heat treatment time shown in Table 2 to manufacture hot-rolled sheets.
  • each of the manufactured hot-rolled plates was cold-rolled at a reduction rate of 80% at room temperature to produce stainless steel sheets.
  • “-” indicates that it was not added intentionally.
  • the Vickers hardness HV ⁇ of the austenite and the Vickers hardness HV ⁇ of the ferrite of the manufactured hot-rolled sheet were measured according to JIS Z 2244: 2009 under a load of 0.01 kgf.
  • the austenite and the ferrite were each measured at five points at the center part in the sheet thickness, and an average value thereof was used as a representative value.
  • an area ratio S ⁇ 001> /S ⁇ 111> which is a ratio of the area proportion S ⁇ 001> of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction to the area proportion S ⁇ 111> of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction was calculated by the following method.
  • the area was calculated from the calculated equivalent circle diameter, the total area of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction and the total area of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction were calculated.
  • the area proportion S′ ⁇ 111 > of the texture of the ferrite with the ⁇ 111> direction oriented in the perpendicular-to-rolling direction and the area proportion S′ ⁇ 001> of the texture of the ferrite with the ⁇ 001> direction oriented in the perpendicular-to-rolling direction with respect to the area of the entire field of view were 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 defined as the area ratio S ⁇ 001> /S ⁇ 111> .
  • the surface waviness height R in the rolling direction of the manufactured dual phase stainless steel was measured by the following method. According to JIS B 0601: 2013, using a surface roughness measuring machine (SV-3000CNC, commercially available from Mitutoyo Corporation), a surface roughness curve of the stainless steel sheet was obtained at a measurement interval of 0.02 mm for a length of 10 mm in the perpendicular-to-rolling direction at the center position of the dual phase stainless steel sheet, and the surface waviness height R in the rolling direction was measured.
  • SV-3000CNC surface roughness measuring machine
  • the appearance was evaluated by visual observation. Specifically, simulating an example of the produced stainless steel sheet and processing for actual use, the surface of the stainless steel sheet that had been subjected to overhang processing with a cylindrical punch was minor-polished, the minor-polished surface was observed in various directions, and the presence of stripe patterns was checked.
  • the appearance was evaluated as very good (A)
  • the appearance was evaluated as good (B)
  • stripe patterns were observed on the stainless steel sheet before a strain of 16% was applied the appearance was evaluated as poor (C).
  • Table 2 shows the evaluation results.
  • underlined values in Table 2 are outside the scope of the present invention.
  • the chemical composition of each of the obtained steel sheet was substantially the same as the chemical composition of each stainless steel.
  • all the steel sheets were dual phase stainless steel sheets.
  • the dual phase stainless steel sheets with an area ratio S ⁇ 001> /S ⁇ 111> of 0.90 to 1.10 had good appearance evaluation results.
  • ⁇ HV of the hot-rolled sheet was 65 or more, and the appearance evaluation result was very good (A). This was thought to be caused by the fact that, since ⁇ HV of the hot-rolled sheet was large, the grain size of the soft phase during cold rolling was subdivided, and as a result, the difference in deformability of the crystal orientation was less likely to occur.

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