WO2018198835A1 - Matériau pour tôle d'acier inoxydable haute résistance laminée à froid et procédé de production associé - Google Patents

Matériau pour tôle d'acier inoxydable haute résistance laminée à froid et procédé de production associé Download PDF

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WO2018198835A1
WO2018198835A1 PCT/JP2018/015579 JP2018015579W WO2018198835A1 WO 2018198835 A1 WO2018198835 A1 WO 2018198835A1 JP 2018015579 W JP2018015579 W JP 2018015579W WO 2018198835 A1 WO2018198835 A1 WO 2018198835A1
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cold
rolled
less
content
steel
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PCT/JP2018/015579
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English (en)
Japanese (ja)
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修司 西田
知洋 石井
正崇 吉野
光幸 藤澤
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Ｊｆｅスチール株式会社
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Priority claimed from JP2018039385A external-priority patent/JP6489254B2/ja
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to CN201880027575.9A priority Critical patent/CN110582589A/zh
Priority to US16/607,170 priority patent/US20200385834A1/en
Priority to EP18792138.2A priority patent/EP3594372A4/fr
Priority to KR1020197030950A priority patent/KR102288000B1/ko
Publication of WO2018198835A1 publication Critical patent/WO2018198835A1/fr

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    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—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
    • C22C38/60—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a material for a stainless cold-rolled steel sheet suitable for producing a ferritic stainless cold-rolled steel sheet having excellent corrosion resistance and further excellent formability and ridging resistance, and a method for producing the same.
  • Ferritic stainless steel sheet does not contain much Ni, so it is cheaper and more price stable than austenitic stainless steel sheet, and it is also a material with excellent rust resistance. It is used for various applications such as transportation equipment and home appliances. In particular, since it has magnetism unlike an austenitic stainless steel sheet, it is increasingly applied to cooking utensils that are compatible with the IH (induction heating) system. Most cooking utensils represented by pans and the like are formed by overhanging. Therefore, sufficient elongation is required for molding into a predetermined shape.
  • the ferritic stainless steel sheet has a problem that surface irregularities (riding) that often impairs the appearance of the surface occur during forming.
  • a polishing step is necessary to remove irregularities after molding. That is, when large ridging occurs, there is a problem that the manufacturing cost increases.
  • ferritic stainless steel sheets tend to have larger ridging as they are subjected to greater strain, i.e., more severely processed.
  • ferritic stainless steel sheets that can be processed more severely than before have been demanded. That is, a ferritic stainless steel sheet having a higher elongation is desired.
  • household cooking utensils are also required to reduce manufacturing costs. That is, a ferritic stainless steel sheet with reduced ridging that causes an increase in manufacturing cost is also required. From these facts, a ferritic stainless steel sheet having a higher elongation and having a sufficiently small ridging even when a larger strain than before is applied.
  • Patent Document 1 in Patent Document 1, C: 0.02 to 0.06%, Si: 1.0% or less, Mn: 1.0% or less, P: 0.05 %: S: 0.01% or less, Al: 0.005% or less, Ti: 0.005% or less, Cr: 11 to 30%, Ni: 0.7% or less, and 0.06 ⁇ ( C + N) ⁇ 0.12, 1 ⁇ N / C and 1.5 ⁇ 10 ⁇ 3 ⁇ (V ⁇ N) ⁇ 1.5 ⁇ 10 ⁇ 2 (C, N, and V represent mass% of each element, respectively)
  • a ferritic stainless steel sheet excellent in formability characterized by satisfying the above requirements is disclosed.
  • Patent Document 2 discloses a ferritic stainless steel sheet containing 0.15% or less C by weight and 13 to 25% Cr, and the hot-rolled sheet of this steel coexists with austenite and ferrite phase 930. By annealing within a range of 10 minutes within a range of ⁇ 990 ° C., the structure becomes a two-phase structure of a martensite phase and a ferrite phase, followed by cold rolling, and annealing a cold-rolled sheet within a range of 750-860 ° C. A method for producing a ferritic stainless steel sheet excellent in ridging resistance and workability is disclosed.
  • Patent Document 3 by mass, C: 0.007 to 0.05%, Si: 0.02 to 0.50%, Mn: 0.05 to 1.0%, P: 0.04% S: 0.01% or less, Cr: 15.5 to 18.0%, Al: 0.001 to 0.10%, N: 0.01 to 0.06%, with the balance being Fe and It has a metal structure composed of inevitable impurities and an area ratio of 10 to 60% of martensite phase and the balance composed of ferrite phase, and the martensite phase has a metal structure composed of ferrite phase. Furthermore, a stainless cold-rolled steel sheet material having a martensite phase hardness of HV500 or less is disclosed.
  • the predistortion added for evaluating ridging is not described.
  • the present inventors produced a plurality of steel plates by the method described in Patent Document 2, and evaluated the ridging height when 23% pre-strain was applied by a ridging evaluation method described later. As a result, no excellent ridging resistance was obtained in any of the steel sheets.
  • the shape of the test piece used for evaluation of elongation is not described. It is a known fact that the elongation value obtained varies depending on the shape of the test piece used for evaluation.
  • the inventors prepared a plurality of steel plates by the method described in Patent Document 2, and evaluated the elongation at break of the steel plates by a tensile test method described later. As a result, excellent formability was not obtained in any steel sheet.
  • the present inventors produced a plurality of steel plates by the method described in Patent Document 3, and evaluated the breaking elongation of the steel plates by a tensile test method described later. As a result, excellent formability was not obtained in any steel sheet.
  • the present invention has been developed in view of the above-described present situation, and is a material for stainless cold-rolled steel sheets suitable for producing ferritic stainless cold-rolled steel sheets having excellent corrosion resistance and excellent formability and ridging resistance. And it aims at providing the manufacturing method.
  • excellent corrosion resistance means that the ridge area ratio measured by the method described below is 30% or less. More preferably, it is 20% or less.
  • the corrosion test for evaluating the corrosion resistance is performed according to JASO M609-91. First, as a test method, the test piece is polished up to No. 600 with emery polishing paper, washed with water, and then ultrasonically degreased in ethanol for 5 minutes. Thereafter, one cycle is salt spray (5% by weight NaCl aqueous solution, 35 ° C.) 2 h ⁇ dry (60 ° C., relative humidity 40%) 4 h ⁇ wet (50 ° C., relative humidity 95% or more) 2 h. To implement. After the test, appearance of the corroded surface is photographed, and the wrinkle area ratio is calculated by image analysis from the obtained photograph for a 30 mm ⁇ 30 mm region at the center of the test piece.
  • excellent formability means that the elongation at break of the steel sheet measured by the method described below is 28% or more. More preferably, it is 32% or more.
  • a JIS No. 13 B tensile test piece is collected.
  • a tensile test based on JIS Z 2241 is performed to measure the elongation at break (El).
  • the three-way average of the obtained elongation at break ((L + 2D + C) / 4, where L, D, and C are the elongation at break (%) in each direction) is calculated as the elongation at break of the steel sheet.
  • excellent ridging resistance means that the ridging height of the steel sheet surface measured by the method described below is 3.0 ⁇ m or less. More preferably, it is 2.5 ⁇ m or less. More preferably, it is 2.0 ⁇ m or less.
  • a JIS No. 5 tensile test piece is taken in parallel with the rolling direction.
  • the surface of the collected test piece is polished with # 600 emery paper, and then 23% tensile strain is applied.
  • the surface shape is measured with a laser displacement meter in the direction perpendicular to the rolling direction on the polished surface of the parallel part of the test piece. The measurement length is 16 mm per line, and the height is measured in increments of 0.05 mm.
  • a total of 50 lines are measured with an interval of each line being 0.1 mm.
  • the obtained shape data of each line is subjected to smoothing and undulation removal processing using a Hanning window function type FIR (Finite Impulse Response) bandpass filter having a high cut filter wavelength of 0.8 mm and a low cut filter wavelength of 8 mm. .
  • FIR Finite Impulse Response
  • the data of 2 mm for each end of each line is excluded, and the arithmetic average waviness Wa defined in JIS B 0601 (2001) is determined for each line. taking measurement.
  • the average value of 50 lines of this arithmetic average waviness Wa is defined as the ridging height of the steel sheet surface.
  • the present inventors provide a material for a stainless steel cold-rolled steel sheet suitable for producing a ferritic stainless steel cold-rolled steel sheet having excellent corrosion resistance and excellent formability and ridging resistance, and a method for producing the same. investigated. As a result, the following knowledge was obtained.
  • a ferritic stainless steel cold-rolled steel sheet excellent in formability and ridging resistance is obtained by using a steel plate material and then performing cold rolling and cold-rolled sheet annealing.
  • the C content is set to 0.030% or less
  • the Cr content is set to 14.4% or less
  • the N content is set to 0.060% or less.
  • the steel ingot having the above components is hot-rolled, followed by hot-rolled sheet annealing at 900 to 1100 ° C., which becomes a ferrite-austenite two-phase region.
  • the steel components are adjusted so that the austenite phase is 10 to 90% in area ratio.
  • almost all of the austenite phase becomes a martensite phase in the cooling process after hot-rolled sheet annealing.
  • the thus obtained hot-rolled annealed sheet (material for cold-rolled steel sheet) containing the martensite phase is then cold-rolled to give colonies that cause ridging (similar crystal orientation).
  • the crystal grain group) is destroyed, and rolling strain is efficiently applied to the ferrite / martensite grain boundary.
  • the rolling strain is efficiently applied as described above, and further, the amount of Cr, C, and N contained in the steel is sufficiently low. Crystals are promoted. Due to the effect of promoting recrystallization, the cold-rolled sheet is sufficiently recrystallized in the temperature range of 780 to 830 ° C. in the ferrite single phase region, and a cold-rolled annealed sheet (ferritic stainless steel cold-rolled) having excellent formability. Steel plate) is obtained.
  • the cold-rolled annealing board has the outstanding ridging resistance by the effect of the colony destruction mentioned above.
  • the present invention is based on the above findings, and the gist of the present invention is as follows.
  • C 0.005 to 0.030%
  • Si 0.05 to 1.00%
  • Mn 0.05 to 1.00%
  • P 0.040% or less
  • S 0.030% or less
  • Al 0.001 to 0.150%
  • Cr 10.8 to 14.4%
  • Ni 0.01-2.50%
  • N 0.005-0.060%
  • a component composition comprising the balance of Fe and unavoidable impurities
  • each element symbol in the above formula (1) represents the content (% by mass) of each element, and the element not contained is 0. [4] Furthermore, in mass%, B: 0.0003 to 0.0030%, Mg: 0.0005 to 0.0100%, Ca: 0.0003 to 0.0030%, Y: 0.01 to 0.20%, and REM (rare earth metal): 0.001 to 0.100%
  • B 0.0003 to 0.0030%
  • Mg 0.0005 to 0.0100%
  • Ca 0.0003 to 0.0030%
  • Y 0.01 to 0.20%
  • REM rare earth metal
  • a material for a stainless steel cold-rolled steel sheet suitable for producing a ferritic stainless steel cold-rolled steel sheet having excellent corrosion resistance and further excellent formability and ridging resistance, and a method for producing the same.
  • the material for stainless steel cold-rolled steel sheet of the present invention is, in mass%, C: 0.005 to 0.030%, Si: 0.05 to 1.00%, Mn: 0.05 to 1.00%, P: 0.040% or less, S: 0.030% or less, Al: 0.001 to 0.150%, Cr: 10.8 to 14.4%, Ni: 0.01 to 2.50%, and N: A structure containing 0.005 to 0.060%, the balance being composed of Fe and inevitable impurities, including a martensite phase with an area ratio of 10 to 90%, and the balance being a ferrite phase
  • a ferritic stainless steel cold-rolled steel sheet of the present invention it is possible to produce a ferritic stainless steel cold-rolled steel sheet having excellent corrosion resistance, and further excellent formability and ridging resistance.
  • % which is a unit of content of a component means the mass% unless there is particular notice.
  • C 0.005 to 0.030%
  • C is an element effective for increasing the strength of steel. Furthermore, C is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. This effect can be obtained by setting the C content to 0.005% or more. However, if the C content exceeds 0.030%, the steel becomes hard and the formability decreases. Therefore, the C content is set to 0.005 to 0.030%.
  • the C content is preferably 0.007% or more, and more preferably 0.010% or more. Further, the C content is preferably 0.020% or less, more preferably 0.015% or less.
  • Si 0.05 to 1.00%
  • Si is an element useful as a deoxidizer. This effect can be obtained by setting the Si content to 0.05% or more. However, if the Si content exceeds 1.00%, the steel becomes hard and the formability decreases. Furthermore, the austenite phase produced
  • Mn 0.05 to 1.00% Mn has a deoxidizing action. Furthermore, Mn is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. These effects can be obtained by making the Mn content 0.05% or more. However, if the Mn content exceeds 1.00%, precipitation and coarsening of MnS are promoted, and this MnS becomes a starting point of rusting and the corrosion resistance is lowered. Therefore, the Mn content is 0.05 to 1.00%. The Mn content is preferably 0.10% or more, more preferably 0.15% or more. Further, the Mn content is preferably 0.80% or less, and more preferably 0.60% or less.
  • P 0.040% or less
  • P is an element that lowers corrosion resistance. Moreover, P reduces hot workability by segregating at the grain boundaries. Therefore, the P content is desirably as low as possible, and is set to 0.040% or less. Preferably, the P content is 0.030% or less.
  • S 0.030% or less S forms Mn and precipitate MnS. This MnS becomes a starting point of pits and causes a decrease in corrosion resistance. Therefore, the lower S content is desirable, and it is 0.030% or less. Preferably, the S content is 0.020% or less.
  • Al 0.001 to 0.150%
  • Al is an effective element for deoxidation. This effect is obtained when the Al content is 0.001% or more. However, if the Al content exceeds 0.150%, the steel becomes hard and the formability decreases. Therefore, the Al content is set to 0.001 to 0.150%.
  • the Al content is preferably 0.005% or more, and more preferably 0.010% or more. Moreover, Al content becomes like this. Preferably it is 0.100% or less, More preferably, it is 0.050% or less.
  • Cr 10.8 to 14.4% Cr is an element that improves the corrosion resistance by forming a passive film on the surface. If the Cr content is less than 10.8%, sufficient corrosion resistance cannot be obtained. On the other hand, if the Cr content exceeds 14.4%, the austenite phase is not sufficiently formed in the steel in the hot-rolled sheet annealing process, the ridging resistance is lowered, the steel is further hardened, and the formability is lowered. . Therefore, the Cr content is 10.8 to 14.4%.
  • the Cr content is preferably 11.0% or more, more preferably 11.5% or more, and further preferably 12.0% or more. Moreover, Cr content becomes like this. Preferably it is 14.0% or less, More preferably, it is 13.5% or less, More preferably, it is 13.0% or less.
  • Ni 0.01-2.50%
  • Ni is an element that suppresses active dissolution in a low pH environment.
  • a so-called gap structure portion in which steel plates are overlapped a low pH environment that easily causes corrosion may be formed.
  • an aqueous solution containing chloride ions that causes the steel plate to become concentrated is concentrated on the steel plate, salt is precipitated from the aqueous solution, A gap structure is formed between the steel sheets, and a low pH environment that easily causes corrosion may be formed.
  • Ni suppresses the progress of corrosion in such an environment and improves the corrosion resistance of steel.
  • Ni has a high effect on crevice corrosion resistance, and remarkably suppresses the progress of corrosion in the active dissolution state, thereby improving the corrosion resistance. Furthermore, Ni is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. This effect is obtained when the Ni content is 0.01% or more. On the other hand, if it exceeds 2.50%, the steel becomes hard and its formability decreases. Therefore, the Ni content is 0.01 to 2.50%.
  • the Ni content is preferably 0.03% or more, more preferably 0.05% or more, and further preferably 0.10% or more. Moreover, Ni content becomes like this. Preferably it is 1.20% or less, More preferably, it is 0.80% or less, More preferably, it is 0.25% or less.
  • N 0.005 to 0.060%
  • N is an element effective for increasing the strength of steel.
  • N is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. This effect can be obtained by making the N content 0.005% or more.
  • the N content is set to 0.005 to 0.060%.
  • the N content is preferably 0.007% or more, and more preferably 0.010% or more.
  • N content becomes like this. Preferably it is 0.020% or less, More preferably, it is 0.015% or less.
  • the balance other than the above components is Fe and inevitable impurities.
  • Typical examples of the inevitable impurities mentioned here include O (oxygen), Zn, Ga, Ge, As, Ag, In, Hf, Ta, Re, Os, Ir, Pt, Au, and Pb.
  • O (oxygen) can be contained in a range of 0.02% or less. About another element, it can contain in 0.1% or less of total.
  • Co 0.01 to 0.50%
  • Co is an element that improves the crevice corrosion resistance of stainless steel. On the other hand, when it contains excessively, the effect will be saturated and workability will fall. Therefore, when Co is contained, the Co content is preferably 0.01 to 0.50%.
  • the Co content is more preferably 0.30% or less, and still more preferably 0.10% or less.
  • Cu 0.01 to 0.80%
  • Cu is an element that reinforces the passive film and improves the corrosion resistance.
  • the content is excessive, the effect is saturated, workability is further lowered, and ⁇ -Cu is liable to precipitate, resulting in a decrease in corrosion resistance. Therefore, when Cu is contained, the Cu content is preferably set to 0.01 to 0.80%.
  • the Cu content is more preferably 0.15% or more, and further preferably 0.40% or more. Further, the Cu content is more preferably 0.60% or less, and further preferably 0.45% or less.
  • Mo 0.01-0.30% Mo has the effect of improving the crevice corrosion resistance of stainless steel. On the other hand, when it contains excessively, the effect will be saturated and workability will fall. Therefore, when Mo is contained, the Mo content is preferably 0.01 to 0.30%. The Mo content is more preferably 0.20% or less, and still more preferably 0.10% or less.
  • W 0.01 to 0.50%
  • W is an element that improves the crevice corrosion resistance of stainless steel.
  • the W content is preferably set to 0.01 to 0.50%.
  • the W content is more preferably 0.03% or more, and even more preferably 0.05% or more.
  • W content becomes like this. More preferably, it is 0.30% or less, More preferably, it is 0.10% or less.
  • Ti 0.01 to 0.30%
  • Ti is an element having a high affinity with C and N, and precipitates as a carbide or nitride during hot rolling to reduce solute C and solute N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • the Ti content is preferably 0.01 to 0.30%.
  • the Ti content is more preferably 0.02% or more. Further, the Ti content is more preferably 0.10% or less, and further preferably 0.08% or less.
  • V 0.01 to 0.10%
  • V is an element having a high affinity with C and N, and precipitates as a carbide or nitride during hot rolling to reduce solid solution C and solid solution N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • generation of the austenite phase in a hot-rolled sheet annealing process will be inhibited, and ridging resistance will fall. Therefore, when V is contained, the V content is preferably 0.01 to 0.10%.
  • the V content is more preferably 0.02% or more, and further preferably 0.03% or more. Further, the V content is more preferably 0.08% or less, and still more preferably 0.05% or less.
  • Zr 0.01 to 0.10%
  • Zr is an element having a high affinity with C and N, and precipitates as carbide or nitride during hot rolling to reduce solid solution C and solid solution N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • the Zr content is preferably 0.01 to 0.10%.
  • the Zr content is more preferably 0.02% or more, and further preferably 0.03% or more. Further, the Zr content is more preferably 0.08% or less, still more preferably 0.05% or less.
  • Nb 0.01-0.30%
  • Nb is an element having a high affinity with C and N, and precipitates as a carbide or nitride during hot rolling to reduce solute C and solute N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • the Nb content is preferably 0.01 to 0.30%.
  • the Nb content is more preferably 0.02% or more. Further, the Nb content is more preferably 0.10% or less, and further preferably 0.08% or less.
  • each element symbol in the above formula (1) represents the content (% by mass) of each element, and the element not contained is 0.
  • the content of each element is as described above in order to obtain excellent ridging resistance.
  • the value of the above formula (1) must be 0.0 or less.
  • Ti, V, Zr, and Nb have an effect of inhibiting the austenite phase generation in the hot-rolled sheet annealing process.
  • B 0.0003 to 0.0030%
  • B is an element effective for preventing embrittlement at low temperature secondary work.
  • the B content is preferably 0.0003 to 0.0030%.
  • the B content is more preferably 0.0005% or more. Further, the B content is more preferably 0.0020% or less.
  • Mg 0.0005 to 0.0100% Mg forms Mg oxide together with Al in molten steel and acts as a deoxidizer. On the other hand, when it contains excessively, the toughness of steel will fall and productivity will fall. Therefore, when Mg is contained, the Mg content is preferably 0.0005 to 0.0100%.
  • the Mg content is more preferably 0.0010% or more. Moreover, Mg content becomes like this. More preferably, it is 0.0050% or less, More preferably, it is 0.0030% or less.
  • Ca 0.0003 to 0.0030%
  • Ca is an element that improves hot workability.
  • the toughness of steel will fall and productivity will fall, and also corrosion resistance will fall by precipitation of CaS. Therefore, when Ca is contained, the Ca content is preferably 0.0003 to 0.0030%.
  • the Ca content is more preferably 0.0010% or more. Further, the Ca content is more preferably 0.0020% or less.
  • Y 0.01-0.20%
  • Y is an element that decreases the viscosity of molten steel and improves cleanliness. On the other hand, when it contains excessively, the effect will be saturated and workability will fall. Therefore, when Y is contained, the Y content is preferably 0.01 to 0.20%. The Y content is more preferably 0.10% or less.
  • REM rare earth metal
  • REM rare earth metal: elements having atomic numbers 57 to 71 such as La, Ce, and Nd
  • the REM content is preferably 0.001 to 0.100%.
  • the REM content is more preferably 0.005% or more.
  • the REM content is more preferably 0.05% or less.
  • Sn 0.001 to 0.500%
  • Sn is effective in improving ridging by promoting deformation band generation during rolling.
  • the Sn content is preferably 0.001 to 0.500%.
  • the Sn content is more preferably 0.003% or more. Further, the Sn content is more preferably 0.200% or less.
  • Sb 0.001 to 0.500%
  • Sb is effective in improving ridging by promoting deformation band generation during rolling.
  • the Sb content is preferably 0.001 to 0.500%.
  • the Sb content is more preferably 0.003% or more.
  • the Sb content is more preferably 0.200% or less.
  • a structure comprising a martensite phase with an area ratio of 10 to 90% and the balance being a ferrite phase
  • a predetermined amount of austenite phase is generated in steel by hot-rolled sheet annealing. Almost all of the austenite phase becomes a martensite phase by being cooled after hot-rolled sheet annealing. Due to the presence of this martensite phase, colonies are destroyed in the cold rolling step, and the ridging resistance of the cold rolled annealing plate is improved. This effect is obtained when the area ratio of the martensite phase after hot-rolled sheet annealing is 10% or more.
  • the area ratio of the martensite phase is 10 to 90%.
  • the area ratio of the martensite phase is preferably 15% or more, more preferably 20% or more.
  • the area ratio of the martensite phase is preferably 70% or less, and more preferably 50% or less.
  • the method for measuring the area ratio of the martensite phase first, a specimen for observation of the structure is collected from the vicinity of the center of the width of the material for cold-rolled steel sheet, and the cross section in the rolling direction is mirror-polished and then Murakami reagent (8 Corrosion (etching) is performed with a mass% KOH-8 mass% [K 3 Fe (CN) 6 ] aqueous solution), and 10 fields of view are photographed at a magnification of 400 times centering on a 1.0 mm portion from the surface layer using an optical microscope.
  • Murakami reagent 8 Corrosion (etching) is performed with a mass% KOH-8 mass% [K 3 Fe (CN) 6 ] aqueous solution
  • the obtained structure photograph is binarized by image analysis, one is regarded as a martensite phase, the other as a ferrite phase, and the martensite phase and the ferrite phase are identified and separated, and the area ratio of the martensite phase is determined. taking measurement. Furthermore, this measurement result is averaged over all 10 visual fields, and the calculated value is defined as the area ratio of the martensite phase.
  • the steel having the above component composition is melted by a known method such as a converter, electric furnace, vacuum melting furnace or the like, and is made into a steel material (steel slab) by a continuous casting method or an ingot-bundling method.
  • This steel material is heated to 1000 ° C. or more and 1200 ° C. or less, and then hot-rolled to a sheet thickness of 2.0 to 6.0 mm under a finishing temperature of 700 ° C. to 1000 ° C.
  • the hot-rolled sheet is annealed by holding the hot-rolled sheet for 5 seconds to 15 minutes in a temperature range of 900 ° C. to 1100 ° C., which is a two-phase region of a ferrite phase and an austenite phase.
  • Hot-rolled sheet annealing is a very important process in obtaining the structure of the present invention.
  • the hot-rolled sheet annealing temperature is less than 900 ° C.
  • annealing is performed in a ferrite single phase region or a temperature region close thereto, and a sufficient amount of austenite phase is not generated in the hot-rolled plate.
  • the hot-rolled sheet annealing temperature exceeds 1100 ° C.
  • annealing is performed in a ferrite single phase region or a temperature region close thereto, and a sufficient amount of austenite phase is not generated in the hot-rolled plate.
  • the time to hold by hot-rolled sheet annealing is less than 5 seconds, a sufficient amount of austenite phase is not generated in the hot-rolled sheet during hot-rolled sheet annealing.
  • hot-rolled sheet annealing is performed by holding at a temperature range of 900 ° C. to 1100 ° C. for 5 seconds to 15 minutes to obtain a hot-rolled annealed sheet.
  • the hot-rolled sheet annealing is preferably performed in a temperature range of 950 ° C. or higher.
  • hot-rolled sheet annealing in the temperature range of 1050 degrees C or less.
  • the hot-rolled sheet annealing is preferably held for 20 seconds or more in the above temperature range.
  • hot-rolled sheet annealing is hold
  • the hot-rolled annealed plate thus produced (stainless steel for cold-rolled steel plate) may then be pickled.
  • a method of manufacturing a ferritic stainless steel cold-rolled steel plate from a hot-rolled annealed plate material for stainless steel cold-rolled steel plate
  • a method of forming a cold-rolled annealed sheet by subjecting the cold-rolled sheet to cold-rolled sheet annealing is exemplified.
  • the cold-rolled annealed plate can be further pickled in a pickling line to remove scale.
  • Skin pass rolling may be performed on the cold-rolled annealed pickled plate from which the scale has been removed.
  • the conditions for the cold rolling need not be particularly defined, and can be performed according to a conventional method.
  • cold rolling with a total rolling reduction of 40 to 90% can be performed.
  • the cold-rolled sheet annealing is preferably a step of holding the cold-rolled sheet in a temperature range of 780 ° C. or higher and 830 ° C. or lower for 5 seconds to 5 minutes.
  • the cold-rolled sheet annealing temperature is 780 ° C. or higher, it is possible to suppress the non-recrystallized structure from remaining in the manufactured ferritic stainless steel cold-rolled steel sheet, and it is possible to further improve the formability.
  • the cold-rolled sheet annealing temperature is 830 ° C or lower, which suppresses the formation of an austenite phase in steel during annealing, suppresses the presence of a martensite phase in the structure after annealing, and improves formability. can do.
  • the holding time in cold-rolled sheet annealing is 5 seconds or more, so that the martensite phase contained in the cold-rolled sheet can be sufficiently decomposed during annealing, and the presence of the martensite phase in the structure after annealing is suppressed. And formability can be further improved.
  • the cold-rolled sheet annealing is preferably performed in a continuous annealing line.
  • Each of the hot-rolled sheets described above is divided into five sheets, and four of them are annealed in the atmosphere at temperatures of 830 to 1200 ° C. shown in Table 1 for 20 seconds, and both the front and back surfaces are ground to obtain a scale. It removed and it was set as the raw material for stainless steel cold-rolled steel plates. Each raw material for cold-rolled steel sheets was sheared and divided at the longitudinal center portion, half was subjected to evaluation described later, and the other half was cold-rolled annealed pickled plate in the following steps. In addition, the remaining one sheet obtained by dividing each hot-rolled sheet was annealed at 800 ° C.
  • Each obtained cold-rolled steel sheet material was then made into a cold-rolled sheet having a sheet thickness of 1.0 mm by cold rolling.
  • the obtained cold-rolled plate was annealed at 800 ° C. for 20 seconds in an air atmosphere to obtain a cold-rolled annealed plate.
  • the obtained cold-rolled annealed plate was pickled by a normal method to obtain a ferritic stainless steel cold-rolled annealed pickled plate.
  • the material for stainless cold-rolled steel sheet and ferritic stainless steel cold-rolled annealed pickled board obtained under the above production conditions were subjected to the evaluation shown below.
  • a specimen for microstructure observation was collected from the vicinity of the center of the width of the cold-rolled steel sheet, and the cross section in the rolling direction was mirror-polished and then Murakami reagent (8 mass% KOH-8 mass% [K 3 Fe (CN) 6 ]).
  • Corrosion (etching) was performed with an aqueous solution, and 10 fields of view were photographed at a magnification of 400 times centering on a portion of 1.0 mm from the surface layer using an optical microscope.
  • the obtained structure photograph was binarized by image analysis, the martensite phase and the ferrite phase were identified and separated, and the area ratio of the martensite phase was measured. The measurement results were averaged over all 10 fields, and the calculated value was defined as the area ratio of the martensite phase.
  • ⁇ Corrosion resistance> Further, a steel sheet having a length of 80 mm and a width of 60 mm was cut from the produced cold-rolled annealed pickling plate by shearing, then the surface was polished to number 600 with emery abrasive paper, washed with water, and then washed in ethanol for 5 minutes. The test piece was obtained by ultrasonic degreasing. A corrosion test was performed on the obtained test piece in accordance with JASO M609-91 to evaluate the corrosion resistance. The test piece was placed in the test apparatus at an inclination of 60 ° with the length direction being vertical after covering the end and the back with vinyl tape.
  • One cycle was salt spray (5 mass% NaCl aqueous solution, 35 ° C.) 2 h ⁇ drying (60 ° C., relative humidity 40%) 4 h ⁇ wet (50 ° C., relative humidity 95% or more) 2 h, and 3 cycles were performed. After the test, appearance of the corroded surface was photographed, and the wrinkle area ratio was calculated from the obtained photograph by image analysis for a 30 mm ⁇ 30 mm region at the center of the test piece. ⁇ The area ratio was 20% or less “ ⁇ ” (pass: excellent), 20% to 30% or less “ ⁇ ” (pass), more than 30% Evaluated as “ ⁇ ” (failed).
  • ⁇ Moldability> Furthermore, from the manufactured cold-rolled annealed pickled plate, a No. 13B test piece defined in JIS Z 2241 is rolled in the rolling direction (L direction), 45 ° direction (D direction) with respect to the rolling direction, and rolling direction. Each sample was sampled so that the direction perpendicular to (C direction) was the length of the test piece, and a tensile test was performed at room temperature in accordance with the same standard to evaluate the moldability.
  • smoothing and swell removal processing were performed using a Hanning window function type FIR (Finite Impulse Response) bandpass filter having a high cut filter wavelength of 0.8 mm and a low cut filter wavelength of 8 mm.
  • FIR Finite Impulse Response
  • the data of 2 mm for each end of each line is excluded, and the arithmetic average waviness Wa defined in JIS B 0601 (2001) is determined for each line. It was measured. The interval between each line was 0.1 mm, and a total of 50 lines were measured. And the average value of 50 lines of this arithmetic mean wave
  • the results obtained are shown in Table 1.
  • the cold rolled annealed pickled plates made from the material for cold rolled steel sheets in which the area ratio of the martensite phase is within the scope of the present invention, i.e., the cold rolled steel sheet material of the present invention example, are all evaluated for corrosion resistance. ”Or“ ⁇ ”, the evaluation of formability is“ ⁇ ”, and the evaluation of ridging resistance is“ ⁇ ”or“ ⁇ ”, which is excellent in corrosion resistance and moldability and ridging resistance. It turned out to be excellent.
  • the material for cold-rolled steel sheets in which the area ratio of the martensite phase is less than the range of the present invention that is, the cold-rolled annealed pickled sheets made from the material for cold-rolled steel sheets of the comparative example, are all ridging resistant.
  • the evaluation is “ ⁇ ”. Since these cold-rolled annealed pickled sheets were insufficient in the amount of martensite phase contained in the material for cold-rolled steel sheets, the colonies were not sufficiently destroyed by cold rolling, so the ridging resistance was poor. It became a thing.
  • the cold-rolled annealed pickled plates produced from the materials for cold-rolled steel sheets according to the present invention each have a corrosion resistance evaluation of “ ⁇ ” or “ ⁇ ”, and a formability evaluation of “ ⁇ ” or “ ⁇ ”.
  • the evaluation of ridging resistance was “ ⁇ ”, “ ⁇ ” or “ ⁇ ”, and it was found that the corrosion resistance was excellent, and the moldability and ridging resistance were also excellent.
  • 2-52 was produced from a comparative cold-rolled steel sheet material having a Ti content higher than the component range of the present invention, and therefore ridging resistance was poor.
  • Test No. 2-55 was produced from the material for the cold rolled steel sheet of the comparative example in which the Cr content is lower than the component range of the present invention and the value of the formula (1) exceeds 0.0. The ridging resistance was poor.
  • Test No. 2-57 was produced from a comparative cold-rolled steel sheet material in which the Nb content was higher than the component range of the present invention, and therefore the ridging resistance was inferior.
  • the material for stainless steel cold-rolled steel sheet of the present invention is suitable for producing a ferritic stainless steel cold-rolled steel sheet having excellent corrosion resistance and excellent formability and ridging resistance.
  • Ferritic stainless steel cold-rolled steel sheets manufactured from the material for stainless steel cold-rolled steel sheets according to the present invention are excellent in corrosion resistance, and are also excellent in formability and ridging resistance. It can be suitably used for applications such as parts for accessories, automobile interior parts, automobile exhaust piping, and building materials.

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Abstract

L'invention concerne : un matériau pour tôle d'acier inoxydable laminée à froid, où ledit matériau se prête à la production d'une tôle d'acier inoxydable ferritique laminée à froid présentant une excellente résistance à la corrosion et une excellente aptitude au moulage et résistance au striage ; et son procédé de production. Le matériau pour tôle d'acier inoxydable laminée à froid selon l'invention a une composition qui comprend, en % en poids, de 0,005 à 0,030 % de C, de 0,05 à 1,00 % de Si, de 0,05 à 1,00 % de Mn, 0,040 % ou moins de P, 0,030 % ou moins de S, de 0,001 à 0,150 % d'Al, de 10,8 à 14,4 % de Cr, de 0,01 à 2,50 % de Ni, et de 0,005 à 0,060 % de N, le reste étant du Fe et d'inévitables impuretés. Le matériau pour tôle d'acier inoxydable laminée à froid a une structure qui comprend, en rapport en surface, de 10 à 90 % de phase martensitique, le reste étant une phase ferritique.
PCT/JP2018/015579 2017-04-25 2018-04-13 Matériau pour tôle d'acier inoxydable haute résistance laminée à froid et procédé de production associé WO2018198835A1 (fr)

Priority Applications (4)

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CN201880027575.9A CN110582589A (zh) 2017-04-25 2018-04-13 不锈钢冷轧钢板用原材及其制造方法
US16/607,170 US20200385834A1 (en) 2017-04-25 2018-04-13 Raw material for cold-rolled stainless steel sheet and method for manufacturing the same
EP18792138.2A EP3594372A4 (fr) 2017-04-25 2018-04-13 Matériau pour tôle d'acier inoxydable haute résistance laminée à froid et procédé de production associé
KR1020197030950A KR102288000B1 (ko) 2017-04-25 2018-04-13 스테인리스 냉연 강판용 소재 및 그 제조 방법

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WO2022085708A1 (fr) * 2020-10-23 2022-04-28 日鉄ステンレス株式会社 Acier inoxydable ferritique et procédé de fabrication d'acier inoxydable ferritique

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Publication number Priority date Publication date Assignee Title
WO2022085708A1 (fr) * 2020-10-23 2022-04-28 日鉄ステンレス株式会社 Acier inoxydable ferritique et procédé de fabrication d'acier inoxydable ferritique
JPWO2022085708A1 (fr) * 2020-10-23 2022-04-28
JP7374338B2 (ja) 2020-10-23 2023-11-06 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびフェライト系ステンレス鋼の製造方法
CN114395692A (zh) * 2022-01-27 2022-04-26 宝钢德盛不锈钢有限公司 一种镜面板用途的200系不锈钢2b冷轧板生产方法
CN114395692B (zh) * 2022-01-27 2023-07-07 宝钢德盛不锈钢有限公司 一种镜面板用途的200系不锈钢2b冷轧板生产方法

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