WO2018198834A1 - Ferritic stainless steel sheet, and production method therefor - Google Patents

Ferritic stainless steel sheet, and production method therefor Download PDF

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Publication number
WO2018198834A1
WO2018198834A1 PCT/JP2018/015578 JP2018015578W WO2018198834A1 WO 2018198834 A1 WO2018198834 A1 WO 2018198834A1 JP 2018015578 W JP2018015578 W JP 2018015578W WO 2018198834 A1 WO2018198834 A1 WO 2018198834A1
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content
hot
stainless steel
steel sheet
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PCT/JP2018/015578
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French (fr)
Japanese (ja)
Inventor
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 JP2018039384A external-priority patent/JP6432701B2/en
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 KR1020197031020A priority Critical patent/KR102286876B1/en
Priority to US16/607,420 priority patent/US11401573B2/en
Priority to CN201880026797.9A priority patent/CN110546293B/en
Publication of WO2018198834A1 publication Critical patent/WO2018198834A1/en

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    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a ferritic stainless steel sheet having excellent corrosion resistance and excellent formability and ridging resistance.
  • 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: 0.005 to 0.035%, Si: 0.25 to less than 0.40%, Mn: 0.05 to 0.35%, P: 0.040 %: S: 0.01% or less, Cr: 15.5 to 18.0%, Al: 0.001 to 0.10%, N: 0.01 to 0.06%, Si and Mn Has disclosed 29.5 ⁇ Si-50 ⁇ Mn + 6 ⁇ 0, and the remainder is made of Fe and inevitable impurities.
  • 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 invention has been developed in view of the above-described present situation, and an object of the present invention is to provide a ferritic stainless steel sheet having excellent corrosion resistance, excellent formability and ridging resistance, and a method for producing the same.
  • 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 have studied a ferritic stainless steel having excellent corrosion resistance, excellent formability and ridging resistance, and a method for producing the same, with respect to the above problems. As a result, the following knowledge was obtained.
  • annealing is performed in a suitable temperature range that is a two-phase region of ferrite phase and austenite phase, and further cold rolling
  • a subsequent ferritic stainless steel sheet having excellent formability and ridging resistance can be obtained by annealing the subsequent steel sheet in an appropriate temperature range for an appropriate time.
  • 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 amount of Cr contained in the steel is sufficiently low, a sufficient amount of austenite phase is generated in the steel sheet during the hot-rolled sheet annealing. This austenite phase becomes a martensite phase during the cooling process after hot-rolled sheet annealing.
  • the hot-rolled annealed sheet containing the martensite phase By rolling the hot-rolled annealed sheet containing the martensite phase in the subsequent cold rolling, colonies (crystal grains having similar crystal orientations) that cause ridging are destroyed, and ferrite / Rolling strain is efficiently imparted to the martensite grain boundary.
  • subsequent cold-rolled sheet annealing in the present invention, as described above, because the rolling distortion is efficiently imparted, further, the amount of Cr, C amount and N amount contained in the steel is sufficiently low, Recrystallization is promoted. Due to the effect of promoting recrystallization, the cold-rolled sheet is sufficiently recrystallized in a temperature range of 780 to 830 ° C. in the ferrite single phase region, and a cold-rolled annealed sheet having excellent formability is obtained. Moreover, 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.
  • the balance has a component composition consisting of Fe and inevitable impurities, A ferritic stainless steel sheet having a breaking elongation of 28% or more and a ridging height of a steel sheet surface imparted with a tensile strain of 23% in the rolling direction is 3.0 ⁇ m 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. [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
  • the ferritic stainless 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: 0.00. 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: 0.00. 005 to 0.060%, the balance is Fe and inevitable impurities, the elongation at break is 28% or more, and the steel sheet surface has a ridging height of 23% in the rolling direction. Is 3.0 ⁇ m or less, and is excellent in corrosion resistance, moldability 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.
  • 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 thus prepared is annealed by hot-rolled sheet holding for 5 seconds to 15 minutes at a temperature range of 900 ° C. or higher and 1100 ° C.
  • Cold-rolled sheet annealing is performed in a temperature range of 780 ° C. or higher and 830 ° C. or lower for 5 seconds to 5 minutes.
  • pickling is performed 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.
  • a process in which hot-rolled sheet annealing is performed by holding a hot-rolled sheet in a temperature range of 900 ° C. to 1100 ° C. for 5 seconds to 15 minutes to form a hot-rolled annealed sheet. Annealing is performed in the phase region or a temperature region close thereto, and a sufficient amount of austenite phase is not formed in the hot-rolled sheet. On the other hand, even when 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.
  • hot-rolled sheet annealing is performed by holding at a temperature range of 900 ° C. to 1100 ° C.
  • the hot-rolled sheet annealing is preferably performed in a temperature range of 950 ° C. or higher. Moreover, it is preferable to perform 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. Moreover, it is preferable that hot-rolled sheet annealing is hold
  • the hot-rolled annealed sheet is cold-rolled to obtain a cold-rolled sheet.
  • the conditions for cold rolling need not be specified, and can be performed according to a conventional method. As an example, in cold rolling, cold rolling with a total rolling reduction of 40 to 90% can be performed.
  • Cold-rolled sheet annealing process in which the cold-rolled sheet is held at a temperature range of 780 ° C. to 830 ° C. for 5 seconds to 5 minutes. If the cold-rolled sheet annealing temperature is less than 780 ° C., an unrecrystallized structure remains in the steel sheet. As a result, sufficient moldability cannot be obtained. On the other hand, when the cold-rolled sheet annealing temperature exceeds 830 ° C., an austenite phase is generated in the steel at the time of annealing, and a martensite phase is present in the structure after annealing, so that sufficient formability cannot be obtained.
  • cold-rolled sheet annealing is performed in a temperature range of 780 ° C. or higher and 830 ° C. or lower for 5 seconds to 5 minutes.
  • Cold-rolled sheet annealing is preferably performed in a temperature range of 790 ° C or higher. Moreover, it is preferable to perform cold-rolled sheet annealing in a temperature range of 810 ° C. or lower. Cold-rolled sheet annealing is preferably maintained for 20 seconds or more in the above temperature range. Moreover, it is preferable that cold-rolled sheet annealing is hold
  • 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 to form hot-rolled annealed sheets. Then, the scale was removed to obtain a material for cold rolling. In addition, the remaining one sheet obtained by dividing each hot-rolled sheet is annealed at 800 ° C. for 8 hours in an air atmosphere to form a hot-rolled annealed sheet, and both the front and back surfaces are ground to remove the scales. The material.
  • Each obtained cold rolling material was then cold rolled into a cold rolled sheet having a thickness of 1.0 mm.
  • 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.
  • a steel plate having a length of 80 mm and a width of 60 mm is cut out from the cold-rolled annealed pickling plate produced above by grinding, then the surface is polished to No. 600 with emery polishing paper, washed with water, and in ethanol for over 5 minutes. Sonic degreasing was performed to obtain a test piece. 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 evaluation of corrosion resistance is “O” or “ ⁇ ”
  • the evaluation of moldability is “O” or “ ⁇ ”
  • the evaluation of ridging resistance is “ ⁇ ” or “O”.
  • Test No. The Comparative Example 2-35 was inferior in corrosion resistance because the Cr content was lower than the component range of the present invention.
  • Test No. The comparative example 2-36 was inferior in ridging resistance because the Cr content was higher than the component range of the present invention.
  • Test No. The Comparative Example 2-37 was inferior in corrosion resistance because the Ni content was lower than the component range of the present invention.
  • Test No. The comparative example of 2-38 was inferior in moldability because the Ni content was higher than the component range of the present invention.
  • the comparative examples 2-40 and 2-42 were inferior in moldability because the contents of C and N were higher than the component range of the present invention.
  • Test No. The comparative example 2-43 was inferior in moldability and ridging resistance because the Si content was higher than the component range of the present invention.
  • Test No. The comparative example 2-44 was inferior in ridging resistance because the Cr content was higher than the component range of the present invention.
  • Test No. The comparative example 2-52 was inferior in ridging resistance because the Ti content was higher than the component range of the present invention.
  • the comparative examples of 2-53, 2-54, and 2-56 were inferior in ridging resistance because the value of the formula (1) exceeded 0.0. Test No.
  • Comparative Example 2-55 the Cr content was lower than the component range of the present invention, and the value of formula (1) exceeded 0.0, so the corrosion resistance and ridging resistance were inferior. Test No. In Comparative Example 2-57, the ridging resistance was inferior because the Nb content was higher than the component range of the present invention.
  • the ferritic stainless steel sheet of the present invention is excellent in corrosion resistance, and further excellent in formability and ridging resistance. It can be suitably used for applications such as piping and building materials.

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Abstract

Provided are: a ferritic stainless steel sheet exhibiting excellent corrosion resistance, mouldability, and ridging resistance; and a production method therefor. This ferritic stainless steel sheet is provided with a component composition which includes, in mass%, 0.005-0.030% of C, 0.05-1.00% of Si, 0.05-1.00% of Mn, 0.040% or less of P, 0.030% or less of S, 0.001-0.150% of Al, 10.8-14.4% of Cr, 0.01-2.50% of Ni, and 0.005-0.060% of N, the remainder comprising Fe and unavoidable impurities. The ferritic stainless steel sheet has an elongation at break of 28% or higher. The ridging height of the surface of the steel sheet to which 23% tensile strain has been applied in the rolling direction is 3.0 µm or lower.

Description

フェライト系ステンレス鋼板およびその製造方法Ferritic stainless steel sheet and manufacturing method thereof
　本発明は、耐食性に優れ、さらに成形性および耐リジング性に優れたフェライト系ステンレス鋼板に関するものである。 The present invention relates to a ferritic stainless steel sheet having excellent corrosion resistance and excellent formability and ridging resistance.
　フェライト系ステンレス鋼板は、多くのＮｉを含有しないことからオーステナイト系ステンレス鋼板に比較して安価で価格安定性に優れた材料であり、さらに耐発銹性に優れた材料であることから、建築材料、輸送機器、家庭電化製品等の様々な用途に使用されている。特に、オーステナイト系ステンレス鋼板と異なり磁性を有することから、ＩＨ（誘導加熱）方式に対応できる調理器具への適用が増えている。鍋などに代表される調理器具は、その多くが張り出し加工によって成形される。そのため、所定の形状への成形には、十分な伸びが必要となる。 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.
　一方、フェライト系ステンレス鋼板には、成形時にしばしば表面に美観を損ねる表面凹凸（リジング）が発生するという問題点がある。表面外観が商品価値を大きく左右する調理器具においては、リジングが発生した場合には、成形の後に凹凸を除去する研磨工程が必要となる。すなわち、大きなリジングが発生すると、製造コストが増加するという課題がある。なお、一般的に、フェライト系ステンレス鋼板には、大きなひずみを加えるほどに、すなわち、厳しい加工を施すほどに、大きなリジングが現れるという傾向がある。 On the other hand, the ferritic stainless steel sheet has a problem that surface irregularities (riding) that often impairs the appearance of the surface occur during forming. In cooking utensils whose surface appearance greatly affects the commercial value, when ridging occurs, 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. In general, ferritic stainless steel sheets tend to have larger ridging as they are subjected to greater strain, i.e., more severely processed.
　近年、家庭用調理器具の形状の多様化に伴い、従来よりも厳しい加工を施すことが可能であるフェライト系ステンレス鋼板が求められている。すなわち、より高い伸びを有するフェライト系ステンレス鋼板が求められている。一方、家庭用調理器具には、製造コストの低廉化も求められている。すなわち、製造コストの増加を招くリジングが低減されたフェライト系ステンレス鋼板も求められている。これらのことから、より高い伸びを有し、かつ、従来よりも大きなひずみを加えた場合にもリジングが十分に小さいフェライト系ステンレス鋼板が求められている。 In recent years, with the diversification of the shape of household cooking utensils, 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. On the other hand, 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.
　上記の課題に対して、例えば、特許文献１では、質量％で、Ｃ：０．０２～０．０６％、Ｓｉ：１．０％以下、Ｍｎ：１．０％以下、Ｐ：０．０５％以下、Ｓ：０．０１％以下、Ａｌ：０．００５％以下、Ｔｉ：０．００５％以下、Ｃｒ：１１～３０％、Ｎｉ：０．７％以下を含み、かつ０．０６≦（Ｃ＋Ｎ）≦０．１２、１≦Ｎ／Ｃおよび１．５×１０－３≦（Ｖ×Ｎ）≦１．５×１０－２（Ｃ、Ｎ、Ｖはそれぞれ各元素の質量％を表す）を満たすことを特徴とする成形性に優れたフェライト系ステンレス鋼板が開示されている。 For example, in 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.
　また、特許文献２では、重量％で０．１５％以下のＣ、１３～２５％のＣｒを含有するフェライト系ステンレス鋼板であって、この鋼の熱延板をオーステナイトおよびフェライト相が共存する９３０～９９０℃の範囲で１０分以内の焼鈍を行うことにより、組織をマルテンサイト相とフェライト相の二相組織とし、次いで、冷間圧延を行い、冷延板を７５０～８６０℃の範囲で焼鈍することを特徴とする耐リジング性と加工性に優れるフェライト系ステンレス鋼板の製造方法が開示されている。 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.
　また、特許文献３では、質量％で、Ｃ：０．００５～０．０３５％、Ｓｉ：０．２５～０．４０未満％、Ｍｎ:０．０５～０．３５％、Ｐ：０．０４０％以下、Ｓ：０．０１％以下、Ｃｒ:１５．５～１８．０％、Ａｌ：０．００１～０．１０％、Ｎ：０．０１～０．０６％を含有し、ＳｉおよびＭｎが２９．５×Ｓｉ－５０×Ｍｎ＋６≧０を満たし、残部がＦｅおよび不可避的不純物からなることを特徴とするフェライト系ステンレス鋼が開示されている。 Further, in Patent Document 3, by mass, C: 0.005 to 0.035%, Si: 0.25 to less than 0.40%, Mn: 0.05 to 0.35%, P: 0.040 %: S: 0.01% or less, Cr: 15.5 to 18.0%, Al: 0.001 to 0.10%, N: 0.01 to 0.06%, Si and Mn Has disclosed 29.5 × Si-50 × Mn + 6 ≧ 0, and the remainder is made of Fe and inevitable impurities.
特許第３５８４８８１号公報Japanese Patent No. 3584881 特公昭４７－１８７８号公報Japanese Patent Publication No.47-1878 特許第５９０４３１０号公報Japanese Patent No. 5904310
　特許文献１に開示された発明においては、２０％の予歪みを加えた試験片をもとにリジングが評価されており、より厳しい加工が施された場合のリジングについて十分な評価がなされていない。本発明者らは、特許文献１に記載された手法で複数の鋼板を作製し、後述する方法にて、２３％の予歪みを加えた場合のリジング高さを評価した。しかしながら、いずれの鋼板においても、優れた耐リジング性は得られなかった。 In the invention disclosed in Patent Document 1, ridging is evaluated based on a test piece to which 20% pre-strain is added, and sufficient evaluation has not been made for ridging when stricter processing is performed. . The inventors produced a plurality of steel plates by the method described in Patent Document 1, and evaluated the ridging height when 23% pre-strain was applied by the method described later. However, no ridging resistance was obtained in any of the steel sheets.
　また、特許文献２に開示された発明においては、リジングを評価するために加えた予歪みが記載されていない。本発明者らは、特許文献２に記載された手法で複数の鋼板を作製し、後述するリジング評価方法にて、２３％の予歪みを加えた場合のリジング高さを評価した。その結果、いずれの鋼板においても、優れた耐リジング性は得られなかった。また、当該の発明においては、伸びの評価に用いた試験片の形状が記載されていない。評価に用いる試験片の形状によって、得られる伸びの値が変化する事は公知の事実である。本発明者らは、特許文献２に記載された手法で複数の鋼板を作製し、後述する引張試験方法にて、鋼板の破断伸びを評価した。その結果、いずれの鋼板においても、優れた成形性は得られなかった。 Further, in the invention disclosed in Patent Document 2, 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. Moreover, in the said invention, 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.
　また、特許文献３に開示された発明においては、２０％の予歪みを加えた試験片をもとにリジングが評価されており、より厳しい加工が施された場合のリジングについて十分な評価がなされていない。本発明者らは、特許文献３に記載された手法で複数の鋼板を作製し、後述する方法にて、２３％の予歪みを加えた場合のリジング高さを評価した。しかしながら、いずれの鋼においても、優れた耐リジング性は得られなかった。 Further, in the invention disclosed in Patent Document 3, ridging is evaluated based on a test piece to which 20% pre-strain is added, and sufficient evaluation is made for ridging when more severe processing is performed. Not. The inventors produced a plurality of steel plates by the method described in Patent Document 3, and evaluated the ridging height when 23% pre-strain was applied by the method described later. However, in any steel, excellent ridging resistance was not obtained.
　本発明は、上記の現状に鑑み開発されたものであって、耐食性に優れ、さらに成形性および耐リジング性に優れるフェライト系ステンレス鋼板およびその製造方法を提供することを目的とする。 The present invention has been developed in view of the above-described present situation, and an object of the present invention is to provide a ferritic stainless steel sheet having excellent corrosion resistance, excellent formability and ridging resistance, and a method for producing the same.
　なお、「優れた耐食性」とは、次に述べる方法で測定した銹面積率が３０％以下であることを意味する。より好ましくは２０％以下である。耐食性を評価するための腐食試験は、ＪＡＳＯ　Ｍ６０９－９１に準拠して実施する。まず、試験方法としては、試験片を、エメリー研磨紙で６００番まで研磨し、水洗後、エタノール中にて５分の超音波脱脂を行う。その後、１サイクルを塩水噴霧（５質量％ＮａＣｌ水溶液、３５℃)２ｈ→乾燥（６０℃、相対湿度４０％）４ｈ→湿潤（５０℃、相対湿度９５％以上）２ｈとし、３サイクルの腐食試験を実施する。試験後、腐食面を外観撮影し、試験片中心の３０ｍｍ×３０ｍｍの領域について、得られた写真から画像解析にて銹面積率を算出する。 In addition, "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.
　また、「優れた成形性」とは、次に述べる方法で測定した鋼板の破断伸びが２８％以上であることを意味する。より好ましくは３２％以上である。破断伸びを評価するために、まずは圧延方向（Ｌ方向）、圧延方向に対して４５度方向（Ｄ方向）、圧延方向に対して直角方向（Ｃ方向）をそれぞれ長手方向とするＪＩＳ　Ｚ　２２４１に準拠したＪＩＳ１３号Ｂ引張試験片を採取する。その後、ＪＩＳ　Ｚ　２２４１に準拠した引張試験を行い、破断伸び（Ｅｌ）をそれぞれ測定する。得られた破断伸びの三方向平均（（Ｌ＋２Ｄ＋Ｃ）／４、ただし、Ｌ、Ｄ、Ｃは各方向の破断伸び（％））を算出し、鋼板の破断伸びとする。 Further, “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. In order to evaluate the elongation at break, first the rolling direction (L direction), 45 degrees direction (D direction) with respect to the rolling direction, and JIS Z 2241 with the direction perpendicular to the rolling direction (C direction) as the longitudinal direction, respectively. A JIS No. 13 B tensile test piece is collected. Thereafter, 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.
　また、「優れた耐リジング性」とは、次に述べる方法で測定した鋼板表面のリジング高さが３．０μｍ以下であることを意味する。より好ましくは２．５μｍ以下である。さらに好ましくは、２．０μｍ以下である。鋼板表面のリジング高さを測定するために、まず、圧延方向に平行にＪＩＳ　５号引張試験片を採取する。次いで、採取した試験片の表面を＃６００のエメリーペーパーを用いて研磨した後、２３％の引張ひずみを付与する。次いで、試験片の平行部の研磨面で、圧延方向に直角の方向に、レーザー変位計で表面形状を測定する。測定長は１ラインあたり１６ｍｍであり、０．０５ｍｍ刻みで高さを測定する。また、各ラインの間隔を０．１ｍｍとして、合計５０ライン測定する。得られた各ラインの形状データは、ハイカットフィルター波長０．８ｍｍ、ローカットフィルター波長８ｍｍとしたＨａｎｎｉｎｇ窓関数型のＦＩＲ（Ｆｉｎｉｔｅ　Ｉｍｐｕｌｓｅ　Ｒｅｓｐｏｎｓｅ）バンドパスフィルターを用いて、それぞれ平滑化およびうねり除去処理を行う。その後、処理を行った各ラインの形状データをもとに、各ラインの両端それぞれ２ｍｍ分のデータを排除して、ＪＩＳ　Ｂ　０６０１（２００１年）で規定される算術平均うねりＷａを各ラインにて測定する。この算術平均うねりＷａの５０ラインの平均値を、鋼板表面のリジング高さとする。
　なお、従来の耐リジング性評価には、１５％あるいは２０％の引張ひずみを付与した試験片が多く用いられている。しかしながら、本発明は、従来よりも複雑な形状へ加工される用途を想定している。そのため、厳しい加工が行われた場合、すなわち、従来よりも多くのひずみが付与された場合を想定し、試験片に付与する引張ひずみを２３％として評価した。 Further, “excellent ridging resistance” means that the ridging height of the steel sheet surface measured by the method described below is 3.0 μm or less. More preferably, it is 2.5 μm or less. More preferably, it is 2.0 μm or less. In order to measure the ridging height of the steel sheet surface, first, a JIS No. 5 tensile test piece is taken in parallel with the rolling direction. Next, the surface of the collected test piece is polished with # 600 emery paper, and then 23% tensile strain is applied. Next, 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. Further, 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. . After that, based on the shape data of each processed line, 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.
In addition, in the conventional evaluation of ridging resistance, many test pieces provided with a tensile strain of 15% or 20% are used. However, the present invention envisages an application that is processed into a more complicated shape than before. Therefore, the case where severe processing was performed, that is, the case where more strain than before was assumed, and the tensile strain applied to the test piece was evaluated as 23%.
　本発明者らは、上記の課題に対し、耐食性に優れ、さらに成形性および耐リジング性に優れたフェライト系ステンレス鋼およびその製造方法を検討した。その結果、以下の知見を得た。
　適切な成分のフェライト系ステンレス鋼に対して、熱間圧延後、冷間圧延する前に、フェライト相とオーステナイト相との二相域となる好適な温度域で焼鈍を行い、さらに、冷間圧延後の鋼板を適切な温度範囲で適切な時間焼鈍することで、成形性および耐リジング性に優れたフェライト系ステンレス鋼板が得られる。 The present inventors have studied a ferritic stainless steel having excellent corrosion resistance, excellent formability and ridging resistance, and a method for producing the same, with respect to the above problems. As a result, the following knowledge was obtained.
For ferritic stainless steel of appropriate components, after hot rolling and before cold rolling, annealing is performed in a suitable temperature range that is a two-phase region of ferrite phase and austenite phase, and further cold rolling A subsequent ferritic stainless steel sheet having excellent formability and ridging resistance can be obtained by annealing the subsequent steel sheet in an appropriate temperature range for an appropriate time.
　具体的には、まず鋼成分のうち、Ｃ含有量を０．０３０％以下とし、かつ、Ｃｒ含有量を１４．４％以下とし、かつ、Ｎ含有量を０．０６０％以下とする。上記成分を有する鋼塊を熱間圧延し、続いてフェライト－オーステナイト二相域となる９００～１１００℃で熱延板焼鈍を行う。本発明においては、鋼中に含まれるＣｒ量が十分に低いために、この熱延板焼鈍時に、鋼板中に十分量のオーステナイト相が生成する。このオーステナイト相は、熱延板焼鈍後の冷却過程でマルテンサイト相となる。続く冷間圧延にて、上記マルテンサイト相を含んだ状態の熱延焼鈍板を圧延することで、リジングの原因となるコロニー（類似した結晶方位を有する結晶粒群）が破壊され、かつ、フェライト／マルテンサイト粒界に圧延歪みが効率的に付与される。続く冷延板焼鈍にて、本発明においては、上述したように圧延歪みが効率的に付与されているため、さらに、鋼中に含まれるＣｒ量、Ｃ量およびＮ量が十分に低いため、再結晶が促進される。再結晶が促進された効果により、７８０～８３０℃のフェライト単相域である温度範囲において、冷延板は十分に再結晶し、優れた成形性を有する冷延焼鈍板が得られる。また、上述したコロニー破壊の効果により、その冷延焼鈍板は優れた耐リジング性を有することとなる。 Specifically, first, among the steel components, the C content is set to 0.030% or less, the Cr content is set to 14.4% or less, and 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. In the present invention, since the amount of Cr contained in the steel is sufficiently low, a sufficient amount of austenite phase is generated in the steel sheet during the hot-rolled sheet annealing. This austenite phase becomes a martensite phase during the cooling process after hot-rolled sheet annealing. By rolling the hot-rolled annealed sheet containing the martensite phase in the subsequent cold rolling, colonies (crystal grains having similar crystal orientations) that cause ridging are destroyed, and ferrite / Rolling strain is efficiently imparted to the martensite grain boundary. In subsequent cold-rolled sheet annealing, in the present invention, as described above, because the rolling distortion is efficiently imparted, further, the amount of Cr, C amount and N amount contained in the steel is sufficiently low, Recrystallization is promoted. Due to the effect of promoting recrystallization, the cold-rolled sheet is sufficiently recrystallized in a temperature range of 780 to 830 ° C. in the ferrite single phase region, and a cold-rolled annealed sheet having excellent formability is obtained. Moreover, the cold-rolled annealing board has the outstanding ridging resistance by the effect of the colony destruction mentioned above.
　本発明は、上記の知見に立脚するものであり、その要旨構成は次のとおりである。
［１］質量％で、
Ｃ：０．００５～０．０３０％、
Ｓｉ：０．０５～１．００％、
Ｍｎ：０．０５～１．００％、
Ｐ：０．０４０％以下、
Ｓ：０．０３０％以下、
Ａｌ：０．００１～０．１５０％、
Ｃｒ：１０．８～１４．４％、
Ｎｉ：０．０１～２．５０％、および
Ｎ：０．００５～０．０６０％
を含有し、残部がＦｅおよび不可避的不純物からなる成分組成を有し、
破断伸びが２８％以上であり、圧延方向に２３％の引張歪みを付与した鋼板表面のリジング高さが３．０μｍ以下である、フェライト系ステンレス鋼板。
［２］さらに、質量％で、
Ｃｏ：０．０１～０．５０％、
Ｃｕ：０．０１～０．８０％、
Ｍｏ：０．０１～０．３０％、および
Ｗ：０．０１～０．５０％
のうちから選んだ１種または２種以上を含有する、［１］に記載のフェライト系ステンレス鋼板。
［３］さらに、質量％で、
Ｔｉ：０．０１～０．３０％、
Ｖ：０．０１～０．１０％、
Ｚｒ：０．０１～０．１０％、および
Ｎｂ：０．０１～０．３０％
のうちから選んだ１種または２種以上を含有し、かつ、
下記式（１）の値が０．０以下である、［１］または［２］に記載のフェライト系ステンレス鋼板。
５４×（Ｔｉ＋Ｖ＋Ｚｒ＋Ｎｂ）－５×Ｍｎ－１９×Ｎｉ＋１．０　・・・式（１）
ただし、上記式（１）における各元素記号は各元素の含有量（質量％）を表し、含有しない元素は０とする。
［４］さらに、質量％で、
Ｂ：０．０００３～０．００３０％、
Ｍｇ：０．０００５～０．０１００％、
Ｃａ：０．０００３～０．００３０％、
Ｙ:０．０１～０．２０％、および
ＲＥＭ（希土類金属）:０．００１～０．１００％
のうちから選んだ１種または２種以上を含有する、［１］～［３］のいずれかに記載のフェライト系ステンレス鋼板。
［５］さらに、質量％で、
Ｓｎ：０．００１～０．５００％、および
Ｓｂ：０．００１～０．５００％
のうちから選んだ１種または２種を含有する、［１］～［４］のいずれかに記載のフェライト系ステンレス鋼板。
［６］上記［１］～［５］のいずれかに記載のフェライト系ステンレス鋼板の製造方法であって、
前記成分組成を有する鋼スラブを熱間圧延し、熱延板とする工程と、
前記熱延板を９００℃以上１１００℃以下の温度範囲で５秒～１５分間保持する熱延板焼鈍を行い、熱延焼鈍板とする工程と、
前記熱延焼鈍板を冷間圧延し、冷延板とする工程と、
前記冷延板を７８０℃以上８３０℃以下の温度範囲で５秒～５分間保持する冷延板焼鈍を行う工程と、
を含む、フェライト系ステンレス鋼板の製造方法。 The present invention is based on the above findings, and the gist of the present invention is as follows.
[1] By 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: 0.01-2.50%, and N: 0.005-0.060%
And the balance has a component composition consisting of Fe and inevitable impurities,
A ferritic stainless steel sheet having a breaking elongation of 28% or more and a ridging height of a steel sheet surface imparted with a tensile strain of 23% in the rolling direction is 3.0 μm or less.
[2] Furthermore, in mass%,
Co: 0.01 to 0.50%,
Cu: 0.01 to 0.80%,
Mo: 0.01 to 0.30% and W: 0.01 to 0.50%
The ferritic stainless steel sheet according to [1], containing one or more selected from among the above.
[3] Furthermore, in mass%,
Ti: 0.01 to 0.30%,
V: 0.01 to 0.10%,
Zr: 0.01 to 0.10%, and Nb: 0.01 to 0.30%
Containing one or more selected from among, and
The ferritic stainless steel sheet according to [1] or [2], wherein the value of the following formula (1) is 0.0 or less.
54 × (Ti + V + Zr + Nb) −5 × Mn−19 × Ni + 1.0 Formula (1)
However, 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%
The ferritic stainless steel sheet according to any one of [1] to [3], containing one or more selected from among the above.
[5] Furthermore, in mass%,
Sn: 0.001 to 0.500%, and Sb: 0.001 to 0.500%
The ferritic stainless steel sheet according to any one of [1] to [4], containing one or two selected from among the above.
[6] A method for producing a ferritic stainless steel sheet according to any one of [1] to [5] above,
Hot-rolling a steel slab having the above-described composition to form a hot-rolled sheet;
Performing the hot-rolled sheet annealing by holding the hot-rolled sheet in a temperature range of 900 ° C. or higher and 1100 ° C. or lower for 5 seconds to 15 minutes,
Cold rolling the hot-rolled annealed plate to form a cold-rolled plate;
Performing cold-rolled sheet annealing by 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;
A method for producing a ferritic stainless steel sheet.
　本発明によれば、耐食性に優れ、さらに成形性と耐リジング性に優れるフェライト系ステンレス鋼板を提供することができる。 According to the present invention, it is possible to provide a ferritic stainless steel sheet that is excellent in corrosion resistance and further excellent in formability and ridging resistance.
　以下、本発明を具体的に説明する。
本発明のフェライト系ステンレス鋼板は、質量％で、Ｃ：０．００５～０．０３０％、Ｓｉ：０．０５～１．００％、Ｍｎ：０．０５～１．００％、Ｐ：０．０４０％以下、Ｓ：０．０３０％以下、Ａｌ：０．００１～０．１５０％、Ｃｒ：１０．８～１４．４％、Ｎｉ：０．０１～２．５０％、およびＮ：０．００５～０．０６０％を含有し、残部がＦｅおよび不可避的不純物からなる成分組成を有し、破断伸びが２８％以上であり、圧延方向に２３％の引張歪みを付与した鋼板表面のリジング高さが３．０μｍ以下であり、耐食性、成形性および耐リジング性に優れる。 Hereinafter, the present invention will be specifically described.
The ferritic stainless 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: 0.00. 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: 0.00. 005 to 0.060%, the balance is Fe and inevitable impurities, the elongation at break is 28% or more, and the steel sheet surface has a ridging height of 23% in the rolling direction. Is 3.0 μm or less, and is excellent in corrosion resistance, moldability and ridging resistance.
　まず、本発明で成分組成を上記の範囲に限定した理由について説明する。なお、成分の含有量の単位である％は、特に断らない限り質量％を意味する。 First, the reason why the component composition is limited to the above range in the present invention will be described. In addition,% which is a unit of content of a component means the mass% unless there is particular notice.
　Ｃ：０．００５～０．０３０％
　Ｃは、鋼の強度を高めるのに有効な元素である。さらに、Ｃは、熱延板焼鈍時のオーステナイト相の生成を促進し、耐リジング性を向上させる元素である。この効果はＣ含有量を０．００５％以上にすることで得られる。しかし、Ｃ含有量が０．０３０％を超えると、鋼が硬質化して成形性が低下する。よって、Ｃ含有量は０．００５～０．０３０％とする。Ｃ含有量は、好ましくは０．００７％以上であり、より好ましくは０．０１０％以上である。また、Ｃ含有量は、好ましくは０．０２０％以下であり、より好ましくは０．０１５％以下である。 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：０．０５～１．００％
　Ｓｉは、脱酸剤として有用な元素である。この効果は、Ｓｉ含有量を０．０５％以上にすることで得られる。しかし、Ｓｉ含有量が１．００％を超えると鋼が硬質化して成形性が低下する。さらに、熱延板焼鈍時に生成するオーステナイト相が減少し、耐リジング性が低下する。従って、Ｓｉ含有量は０．０５～１．００％とする。Ｓｉ含有量は、好ましくは０．０７％以上であり、より好ましくは０．１０％以上であり、さらに好ましくは０．２０％以上である。また、Ｓｉ含有量は、好ましくは０．５０％以下であり、より好ましくは０．４０％未満であり、さらに好ましくは０．３０％未満である。 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 | generated at the time of hot-rolled sheet annealing reduces, and ridging resistance falls. Therefore, the Si content is 0.05 to 1.00%. Si content becomes like this. Preferably it is 0.07% or more, More preferably, it is 0.10% or more, More preferably, it is 0.20% or more. Moreover, Si content becomes like this. Preferably it is 0.50% or less, More preferably, it is less than 0.40%, More preferably, it is less than 0.30%.
　Ｍｎ：０．０５～１．００％
　Ｍｎには、脱酸作用がある。さらに、Ｍｎは、熱延板焼鈍時のオーステナイト相の生成を促進し、耐リジング性を向上させる元素である。これらの効果は、Ｍｎ含有量を０．０５％以上にすることで得られる。しかし、Ｍｎ含有量が１．００％を超えるとＭｎＳの析出および粗大化が促進され、このＭｎＳが発銹の起点となって耐食性が低下する。従って、Ｍｎ含有量は０．０５～１．００％とする。Ｍｎ含有量は、好ましくは０．１０％以上であり、より好ましくは０．１５％以上である。また、Ｍｎ含有量は、好ましくは０．８０％以下であり、より好ましくは０．６０％以下である。 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％以下
　Ｐは耐食性を低下させる元素である。また、Ｐは結晶粒界に偏析することで熱間加工性を低下させる。そのため、Ｐ含有量は可能な限り低いほうが望ましく、０．０４０％以下とする。好ましくは、Ｐ含有量は０．０３０％以下である。 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％以下
　ＳはＭｎと析出物ＭｎＳを形成する。このＭｎＳは食孔の起点となり、耐食性の低下を招く。よって、Ｓ含有量は低いほうが望ましく、０．０３０％以下とする。好ましくは、Ｓ含有量は０．０２０％以下である。 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：０．００１～０．１５０％
　Ａｌは、脱酸のために有効な元素である。この効果は、Ａｌ含有量が０．００１％以上で得られる。しかし、Ａｌ含有量が０．１５０％を超えると鋼が硬質化し成形性が低下する。従って、Ａｌ含有量は０．００１～０．１５０％とする。Ａｌ含有量は、好ましくは０．００５％以上であり、より好ましくは０．０１０％以上である。また、Ａｌ含有量は、好ましくは０．１００％以下であり、より好ましくは０．０５０％以下である。 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：１０．８～１４．４％
　Ｃｒは、表面に不働態皮膜を形成して耐食性を高める元素である。Ｃｒ含有量が１０．８％未満では十分な耐食性が得られない。一方、Ｃｒ含有量が１４．４％を超えると、熱延板焼鈍工程において鋼中にオーステナイト相が十分に生成せず、耐リジング性が低下し、さらに鋼が硬質化して成形性が低下する。よって、Ｃｒ含有量は１０．８～１４．４％とする。Ｃｒ含有量は、好ましくは１１．０％以上であり、より好ましくは１１．５％以上であり、さらに好ましくは１２．０％以上である。また、Ｃｒ含有量は、好ましくは１４．０％以下であり、より好ましくは１３．５％以下であり、さらに好ましくは１３．０％以下である。 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は、低ｐＨ環境において、活性溶解を抑制する元素である。鋼板同士が重ね合わせになった、いわゆる隙間構造部においては、腐食を引き起こしやすい低ｐＨ環境が形成されることがある。また、上述した鋼板同士の間に形成される隙間構造部以外においても、鋼板の発銹を招く塩化物イオンを含む水溶液が鋼板上にて濃化し、水溶液中から塩が析出し、析出塩と鋼板の間に隙間構造が形成され、腐食を引き起こしやすい低ｐＨ環境が形成されることがある。Ｎｉは、そのような環境における腐食の進行を抑制して、鋼の耐食性を向上させる。すなわちＮｉは、耐隙間腐食性に効果が高く、活性溶解状態における腐食の進行を顕著に抑制して耐食性を向上させる。さらに、Ｎｉは、熱延板焼鈍時のオーステナイト相の生成を促進し、耐リジング性を向上させる元素である。
　この効果は、Ｎｉ含有量が０．０１％以上で得られる。一方、２．５０％を超えると鋼が硬質化してその成形性が低下する。従って、Ｎｉ含有量は０．０１～２．５０％とする。Ｎｉ含有量は、好ましくは０．０３％以上であり、より好ましくは０．０５％以上であり、さらに好ましくは０．１０％以上である。また、Ｎｉ含有量は、好ましくは１．２０％以下であり、より好ましくは０．８０％以下であり、さらに好ましくは０．２５％以下である。 Ni: 0.01-2.50%
Ni is an element that suppresses active dissolution in a low pH environment. In a so-called gap structure portion in which steel plates are overlapped, a low pH environment that easily causes corrosion may be formed. In addition to the gap structure formed between the steel plates described above, 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. That is, 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：０．００５～０．０６０％
　Ｎは、鋼の強度を高めるのに有効な元素である。さらに、Ｎは、熱延板焼鈍時のオーステナイト相の生成を促進し、耐リジング性を向上させる元素である。この効果はＮ含有量を０．００５％以上にすることで得られる。しかし、Ｎ含有量が０．０６０％を超えると、鋼が硬質化して成形性が低下する。よって、Ｎ含有量は０．００５～０．０６０％とする。Ｎ含有量は、好ましくは０．００７％以上であり、より好ましくは０．０１０％以上である。また、Ｎ含有量は、好ましくは０．０２０％以下であり、より好ましくは０．０１５％以下である。 N: 0.005 to 0.060%
N is an element effective for increasing the strength of steel. Furthermore, 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. However, if the N content exceeds 0.060%, the steel becomes hard and the formability decreases. Therefore, 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. Moreover, N content becomes like this. Preferably it is 0.020% or less, More preferably, it is 0.015% or less.
　以上の成分以外の残部はＦｅおよび不可避的不純物である。ここで言う不可避的不純物の代表例には、Ｏ（酸素）、Ｚｎ、Ｇａ、Ｇｅ、Ａｓ、Ａｇ、Ｉｎ、Ｈｆ、Ｔａ、Ｒｅ、Ｏｓ、Ｉｒ、Ｐｔ、Ａｕ、Ｐｂなどがある。これらの元素のうち、Ｏ（酸素）は０．０２％以下の範囲で含むことができる。その他の元素については、合計で０．１％以下の範囲で含むことができる。 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. Among these elements, 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.
　本発明では上述した基本成分の他にも、以下に述べる元素を適宜含有させることができる。 In the present invention, in addition to the basic components described above, the following elements can be appropriately contained.
　Ｃｏ：０．０１～０．５０％
　Ｃｏは、ステンレス鋼の耐隙間腐食性を向上させる元素である。一方、過剰に含有すると、その効果は飽和し、さらに、加工性が低下する。そのため、Ｃｏを含有する場合は、Ｃｏ含有量を０．０１～０．５０％とすることが好ましい。Ｃｏ含有量は、より好ましくは０．３０％以下であり、さらに好ましくは０．１０％以下である。 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：０．０１～０．８０％
　Ｃｕは不働態皮膜を強化し、耐食性を向上させる元素である。一方、過剰に含有するとその効果は飽和し、さらに加工性が低下するとともに、ε－Ｃｕが析出しやすくなり、耐食性が低下する。そのため、Ｃｕを含有する場合は、Ｃｕ含有量を０．０１～０．８０％とすることが好ましい。Ｃｕ含有量は、より好ましくは０．１５％以上であり、さらに好ましくは０．４０％以上である。また、Ｃｕ含有量は、より好ましくは０．６０％以下であり、さらに好ましくは０．４５％以下である。 Cu: 0.01 to 0.80%
Cu is an element that reinforces the passive film and improves the corrosion resistance. On the other hand, when the content is excessive, the effect is saturated, workability is further lowered, and ε-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には、ステンレス鋼の耐隙間腐食性を向上させる効果がある。一方、過剰に含有するとその効果は飽和し、さらに加工性が低下する。そのため、Ｍｏを含有する場合は、Ｍｏ含有量を０．０１～０．３０％とすることが好ましい。Ｍｏ含有量は、より好ましくは０．２０％以下であり、さらに好ましくは０．１０％以下である。 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：０．０１～０．５０％
　Ｗは、ステンレス鋼の耐隙間腐食性の向上させる元素である。一方、過剰に含有するとその効果は飽和し、さらに、加工性が低下する。そのため、Ｗを含有する場合は、Ｗ含有量を０．０１～０．５０％とすることが好ましい。Ｗ含有量は、より好ましくは０．０３％以上であり、さらに好ましくは０．０５％以上である。また、Ｗ含有量は、より好ましくは０．３０％以下であり、さらに好ましくは０．１０％以下である。 W: 0.01 to 0.50%
W 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 W is contained, 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. Moreover, W content becomes like this. More preferably, it is 0.30% or less, More preferably, it is 0.10% or less.
　Ｔｉ：０．０１～０．３０％
　Ｔｉは、ＣおよびＮとの親和力の高い元素であり、熱間圧延時に炭化物あるいは窒化物として析出し、母相中の固溶Ｃおよび固溶Ｎを低減させ、冷延板焼鈍後の加工性を向上させる効果がある。一方、過剰に含有すると、熱延板焼鈍工程におけるオーステナイト相の生成を阻害し、耐リジング性が低下する。そのため、Ｔｉを含有する場合は、Ｔｉ含有量を０．０１～０．３０％とすることが好ましい。Ｔｉ含有量は、より好ましくは０．０２％以上である。また、Ｔｉ含有量は、より好ましくは０．１０％以下であり、さらに好ましくは０．０８％以下である。 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. On the other hand, when it contains excessively, the production | generation of the austenite phase in a hot-rolled sheet annealing process will be inhibited, and ridging resistance will fall. Therefore, when Ti is contained, 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：０．０１～０．１０％
　Ｖは、ＣおよびＮとの親和力の高い元素であり、熱間圧延時に炭化物あるいは窒化物として析出し、母相中の固溶Ｃおよび固溶Ｎを低減させ、冷延板焼鈍後の加工性を向上させる効果がある。一方、過剰に含有すると、熱延板焼鈍工程におけるオーステナイト相の生成を阻害し、耐リジング性が低下する。そのため、Ｖを含有する場合は、Ｖ含有量を０．０１～０．１０％とすることが好ましい。Ｖ含有量は、より好ましくは０．０２％以上であり、さらに好ましくは０．０３％以上である。また、Ｖ含有量は、より好ましくは０．０８％以下であり、さらに好ましくは０．０５％以下である。 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. On the other hand, when it contains excessively, the production | 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：０．０１～０．１０％
　Ｚｒは、ＣおよびＮとの親和力の高い元素であり、熱間圧延時に炭化物あるいは窒化物として析出し、母相中の固溶Ｃおよび固溶Ｎを低減させ、冷延板焼鈍後の加工性を向上させる効果がある。一方、過剰に含有すると、熱延板焼鈍工程におけるオーステナイト相の生成を阻害し、耐リジング性が低下する。そのため、Ｚｒを含有する場合は、Ｚｒ含有量を０．０１～０．１０％とすることが好ましい。Ｚｒ含有量は、より好ましくは０．０２％以上であり、さらに好ましくは０．０３％以上である。また、Ｚｒ含有量は、より好ましくは０．０８％以下であり、さらに好ましくは０．０５％以下である。 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. On the other hand, when it contains excessively, the production | generation of the austenite phase in a hot-rolled sheet annealing process will be inhibited, and ridging resistance will fall. Therefore, when Zr is contained, 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は、ＣおよびＮとの親和力の高い元素であり、熱間圧延時に炭化物あるいは窒化物として析出し、母相中の固溶Ｃおよび固溶Ｎを低減させ、冷延板焼鈍後の加工性を向上させる効果がある。一方、過剰に含有すると、熱延板焼鈍工程におけるオーステナイト相の生成を阻害し、耐リジング性が低下する。そのため、Ｎｂを含有する場合は、Ｎｂ含有量を０．０１～０．３０％とすることが好ましい。Ｎｂ含有量は、より好ましくは０．０２％以上である。また、Ｎｂ含有量は、より好ましくは０．１０％以下であり、さらに好ましくは０．０８％以下である。 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. On the other hand, when it contains excessively, the production | generation of the austenite phase in a hot-rolled sheet annealing process will be inhibited, and ridging resistance will fall. Therefore, when Nb is contained, 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.
　Ｔｉ、Ｖ、Ｚｒ、Ｎｂのうちから選んだ１種または２種以上を含有する場合には下記式（１）の値が０．０以下である
５４×（Ｔｉ＋Ｖ＋Ｚｒ＋Ｎｂ）－５×Ｍｎ－１９×Ｎｉ＋１．０　・・・式（１）
ただし、上記式（１）における各元素記号は各元素の含有量（質量％）を表し、含有しない元素は０とする。
　本発明を実施するにあたり、Ｔｉ、Ｖ、Ｚｒ、Ｎｂのうちから選んだ１種または２種以上を含有する場合には、優れた耐リジング性を得るためには、各元素の含有量が上述の範囲を満たすとともに、上記式（１）の値を０．０以下とすることが必要である。
　上述したように、Ｔｉ、Ｖ、Ｚｒ、Ｎｂには、熱延板焼鈍工程におけるオーステナイト相の生成を阻害する作用がある。一方、これらの元素を含有する場合にも、オーステナイト相の生成を促進するＭｎおよびＮｉの含有量を十分に高めることで、熱延板焼鈍工程において鋼中に十分量のオーステナイト相を生成させることができる。
　すなわち、Ｔｉ、Ｖ、Ｚｒ、Ｎｂのうちから選んだ１種または２種以上を含有する場合には、式（１）の値が０．０以下となるように鋼成分を調整することで、熱延板焼鈍時に十分量のオーステナイト相を熱延板中に生成させ、熱延焼鈍板中に十分量のマルテンサイト相を存在させることが可能となり、冷延工程においてコロニーの破壊を十分として、冷延焼鈍板に優れた耐リジング性を付与する事ができる。一方、式（１）の値が０．０を超える場合、熱延板焼鈍時に十分量のオーステナイト相が熱延板中に生成せず、熱延焼鈍板中に十分量のマルテンサイト相が存在しないこととなり、冷延工程においてコロニーの破壊が不十分となり、冷延焼鈍板の耐リジング性が劣る事となる。 When one or more selected from Ti, V, Zr, and Nb are contained, the value of the following formula (1) is 0.0 or less: 54 × (Ti + V + Zr + Nb) −5 × Mn−19 × Ni + 1.0 Formula (1)
However, each element symbol in the above formula (1) represents the content (% by mass) of each element, and the element not contained is 0.
In carrying out the present invention, when one or more selected from Ti, V, Zr, and Nb are contained, the content of each element is as described above in order to obtain excellent ridging resistance. In addition, the value of the above formula (1) must be 0.0 or less.
As described above, Ti, V, Zr, and Nb have an effect of inhibiting the austenite phase generation in the hot-rolled sheet annealing process. On the other hand, even when these elements are contained, by sufficiently increasing the contents of Mn and Ni that promote the formation of the austenite phase, a sufficient amount of austenite phase is generated in the steel in the hot-rolled sheet annealing process. Can do.
That is, when containing one or more selected from Ti, V, Zr, and Nb, by adjusting the steel components so that the value of the formula (1) is 0.0 or less, A sufficient amount of austenite phase is generated in the hot-rolled sheet during hot-rolled sheet annealing, and a sufficient amount of martensite phase can be present in the hot-rolled annealed sheet. Excellent ridging resistance can be imparted to the cold-rolled annealed sheet. On the other hand, when the value of formula (1) exceeds 0.0, a sufficient amount of austenite phase is not generated in the hot-rolled sheet during hot-rolled sheet annealing, and a sufficient amount of martensite phase is present in the hot-rolled annealed sheet. In other words, the colony is not sufficiently destroyed in the cold rolling process, and the ridging resistance of the cold rolled annealed sheet is inferior.
　Ｂ：０．０００３～０．００３０％
　Ｂは、低温二次加工脆化を防止するのに有効な元素である。一方、過剰に含有すると熱間加工性が低下する。そのため、Ｂを含有する場合は、Ｂ含有量を０．０００３～０．００３０％とすることが好ましい。Ｂ含有量は、より好ましくは０．０００５％以上である。また、Ｂ含有量は、より好ましくは０．００２０％以下である。 B: 0.0003 to 0.0030%
B is an element effective for preventing embrittlement at low temperature secondary work. On the other hand, when it contains excessively, hot workability will fall. Therefore, when B is contained, 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：０．０００５～０．０１００％
　Ｍｇは、溶鋼中でＡｌとともにＭｇ酸化物を形成し脱酸剤として作用する。一方、過剰に含有すると鋼の靱性が低下して生産性が低下する。そのため、Ｍｇを含有する場合は、Ｍｇ含有量を０．０００５～０．０１００％とすることが好ましい。Ｍｇ含有量は、より好ましくは０．００１０％以上である。また、Ｍｇ含有量は、より好ましくは０．００５０％以下であり、さらに好ましくは０．００３０％以下である。 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：０．０００３～０．００３０％
　Ｃａは、熱間加工性を向上させる元素である。一方、過剰に含有すると鋼の靱性が低下して生産性が低下し、さらに、ＣａＳの析出により耐食性が低下する。そのため、Ｃａを含有する場合は、Ｃａ含有量を０．０００３～０．００３０％とすることが好ましい。Ｃａ含有量は、より好ましくは０．００１０％以上である。また、Ｃａ含有量は、より好ましくは０．００２０％以下である。 Ca: 0.0003 to 0.0030%
Ca is an element that improves hot workability. On the other hand, when it contains excessively, 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は、溶鋼の粘度を減少させ、清浄度を向上させる元素である。一方、過剰に含有するとその効果は飽和し、さらに、加工性が低下する。そのため、Ｙを含有する場合は、Ｙ含有量を０．０１～０．２０％とすることが好ましい。Ｙ含有量は、より好ましくは０．１０％以下である。 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（希土類金属）：０．００１～０．１００％
　ＲＥＭ（希土類金属：Ｌａ、Ｃｅ、Ｎｄなどの原子番号５７～７１の元素）は、耐高温酸化性を向上させる元素である。一方、過剰に含有するとその効果は飽和し、さらに、熱間圧延の際に表面欠陥が生じ、生産性が低下する。そのため、ＲＥＭを含有する場合は、ＲＥＭ含有量を０．００１～０．１００％とすることが好ましい。ＲＥＭ含有量は、より好ましくは０．００５％以上である。また、ＲＥＭ含有量は、より好ましくは０．０５％以下である。 REM (rare earth metal): 0.001 to 0.100%
REM (rare earth metal: elements having atomic numbers 57 to 71 such as La, Ce, and Nd) is an element that improves high-temperature oxidation resistance. On the other hand, if contained excessively, the effect is saturated, and further, surface defects occur during hot rolling, and productivity is lowered. Therefore, when REM is contained, 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：０．００１～０．５００％
　Ｓｎは、圧延時における変形帯生成の促進によるリジング向上に効果的である。一方、過剰に含有するとその効果は飽和し、さらに成形性が低下する。そのため、Ｓｎを含有する場合は、Ｓｎ含有量を０．００１～０．５００％とすることが好ましい。Ｓｎ含有量は、より好ましくは０．００３％以上である。また、Ｓｎ含有量は、より好ましくは０．２００％以下である。 Sn: 0.001 to 0.500%
Sn is effective in improving ridging by promoting deformation band generation during rolling. On the other hand, when it contains excessively, the effect will be saturated and a moldability will fall. Therefore, when Sn is contained, 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：０．００１～０．５００％
　Ｓｂは、圧延時における変形帯生成の促進によるリジング向上に効果的である。一方、過剰に含有するとその効果は飽和し、さらに成形性が低下する。そのため、Ｓｂを含有する場合は、Ｓｂ含有量を０．００１～０．５００％とすることが好ましい。Ｓｂ含有量は、より好ましくは０．００３％以上である。また、Ｓｂ含有量は、より好ましくは０．２００％以下である。 Sb: 0.001 to 0.500%
Sb is effective in improving ridging by promoting deformation band generation during rolling. On the other hand, when it contains excessively, the effect will be saturated and a moldability will fall. Therefore, when Sb is contained, 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.
　次に本発明のフェライト系ステンレス鋼板の好適な製造方法について説明する。上記した成分組成の鋼を、転炉、電気炉、真空溶解炉等の公知の方法で溶製し、連続鋳造法あるいは造塊－分塊法により鋼素材（鋼スラブ）とする。この鋼素材を１０００℃以上１２００℃以下に加熱後、仕上温度を７００℃以上１０００℃以下の条件で、板厚２．０～６．０ｍｍになるように熱間圧延する。こうして作製した熱延板を９００℃以上１１００℃以下の温度範囲で５秒～１５分間保持する熱延板焼鈍をして酸洗を行い、次に、冷間圧延を行い、連続焼鈍ラインにて７８０℃以上８３０℃以下の温度範囲で５秒～５分間保持する冷延板焼鈍を行う。冷延板焼鈍後には、酸洗ラインにて酸洗を行い、スケールを除去する。スケールを除去した冷延焼鈍酸洗板にはスキンパス圧延を行ってもよい。 Next, a preferred method for producing the ferritic stainless steel sheet of the present invention will be described. 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 thus prepared is annealed by hot-rolled sheet holding for 5 seconds to 15 minutes at a temperature range of 900 ° C. or higher and 1100 ° C. or lower, and then cold-rolled and then subjected to continuous annealing in Cold-rolled sheet annealing is performed in a temperature range of 780 ° C. or higher and 830 ° C. or lower for 5 seconds to 5 minutes. After cold-rolled sheet annealing, pickling is performed 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.
　熱延板を９００℃以上１１００℃以下の温度範囲で５秒～１５分間保持する熱延板焼鈍を行い、熱延焼鈍板とする工程
　熱延板焼鈍温度が９００℃未満であると、フェライト単相域あるいはそれに近い温度域での焼鈍となり、熱延板中に十分な量のオーステナイト相が生成しない。一方、熱延板焼鈍温度が１１００℃を超えた場合にも、フェライト単相域あるいはそれに近い温度域での焼鈍となり、熱延板中に十分な量のオーステナイト相が生成しない。
また、熱延板焼鈍で保持する時間が５秒未満であると、熱延板焼鈍の間に熱延板中に十分量のオーステナイト相が生成しない。一方、熱延板焼鈍で保持する時間が１５分超えであると、熱延板焼鈍の間に結晶粒が粗大となり、その後の冷延焼鈍にて得られる冷延焼鈍板の結晶粒の粗大化を招く。このような組織は、加工時に、オレンジピールと呼ばれるリジングとは異なる肌荒れを招くことになる。
よって、本発明では、９００℃以上１１００℃以下の温度範囲で５秒～１５分間保持する熱延板焼鈍を行い、熱延焼鈍板を得る。熱延板焼鈍は、９５０℃以上の温度範囲で行うことが好ましい。また、熱延板焼鈍は、１０５０℃以下の温度範囲で行うことが好ましい。熱延板焼鈍は、上記温度範囲で２０秒以上保持することが好ましい。また、熱延板焼鈍は、上記温度範囲で１分以下保持することが好ましい。 A process in which hot-rolled sheet annealing is performed by holding a hot-rolled sheet in a temperature range of 900 ° C. to 1100 ° C. for 5 seconds to 15 minutes to form a hot-rolled annealed sheet. Annealing is performed in the phase region or a temperature region close thereto, and a sufficient amount of austenite phase is not formed in the hot-rolled sheet. On the other hand, even when 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.
Moreover, when 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. On the other hand, if the holding time in hot-rolled sheet annealing exceeds 15 minutes, the crystal grains become coarse during hot-rolled sheet annealing, and the coarsened crystal grains of the cold-rolled annealed sheet obtained by subsequent cold-rolled annealing Invite. Such a structure causes rough skin different from ridging called orange peel at the time of processing.
Therefore, in the present invention, 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. Moreover, it is preferable to perform 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. Moreover, it is preferable that hot-rolled sheet annealing is hold | maintained for 1 minute or less within the said temperature range.
　その後、熱延焼鈍板を冷間圧延し、冷延板とする。なお、冷間圧延の条件は特に規定する必要はなく、常法にしたがって行うことができる。一例として、冷間圧延では、総圧下率を４０～９０％とする冷間圧延を施すことができる。 Thereafter, the hot-rolled annealed sheet is cold-rolled to obtain a cold-rolled sheet. The conditions for cold rolling need not be specified, and can be performed according to a conventional method. As an example, in cold rolling, cold rolling with a total rolling reduction of 40 to 90% can be performed.
　冷延板を７８０℃以上８３０℃以下の温度範囲で５秒～５分間保持する冷延板焼鈍を行う工程
　冷延板焼鈍温度が７８０℃未満であると、鋼板中に未再結晶組織が残存する事となり、十分な成形性が得られない。一方、冷延板焼鈍温度が８３０℃超えであると、焼鈍時に鋼中にオーステナイト相が生成し、焼鈍後の組織にマルテンサイト相が存在する事となり、十分な成形性が得られない。
また、冷延板焼鈍で保持する時間が５秒未満であると、冷延板に含まれるマルテンサイト相の一部が焼鈍時に分解せず、焼鈍後の組織にマルテンサイト相が存在する事となり、十分な成形性が得られない。
一方、冷延板焼鈍で保持する時間が５分超えであると、冷延板焼鈍の間に結晶粒が粗大となり、冷延焼鈍後の鋼板の加工時に、オレンジピールと呼ばれるリジングとは異なる肌荒れを招くこととなる。
よって、本発明では、７８０℃以上８３０℃以下の温度範囲で５秒～５分間保持する冷延板焼鈍を行う。冷延板焼鈍は、７９０℃以上の温度範囲で行うことが好ましい。また、冷延板焼鈍は、８１０℃以下の温度範囲で行うことが好ましい。冷延板焼鈍は、上記温度範囲で２０秒以上保持することが好ましい。また、冷延板焼鈍は、上記温度範囲で１分以下保持することが好ましい。 Cold-rolled sheet annealing process in which the cold-rolled sheet is held at a temperature range of 780 ° C. to 830 ° C. for 5 seconds to 5 minutes. If the cold-rolled sheet annealing temperature is less than 780 ° C., an unrecrystallized structure remains in the steel sheet. As a result, sufficient moldability cannot be obtained. On the other hand, when the cold-rolled sheet annealing temperature exceeds 830 ° C., an austenite phase is generated in the steel at the time of annealing, and a martensite phase is present in the structure after annealing, so that sufficient formability cannot be obtained.
In addition, if the holding time in cold-rolled sheet annealing is less than 5 seconds, a part of the martensite phase contained in the cold-rolled sheet does not decompose during annealing, and the martensite phase exists in the structure after annealing. However, sufficient moldability cannot be obtained.
On the other hand, if the holding time in cold-rolled sheet annealing is longer than 5 minutes, the crystal grains become coarse during cold-rolled sheet annealing, and when roughing the steel sheet after cold-rolled annealing, rough skin different from ridging called orange peel Will be invited.
Therefore, in the present invention, cold-rolled sheet annealing is performed in a temperature range of 780 ° C. or higher and 830 ° C. or lower for 5 seconds to 5 minutes. Cold-rolled sheet annealing is preferably performed in a temperature range of 790 ° C or higher. Moreover, it is preferable to perform cold-rolled sheet annealing in a temperature range of 810 ° C. or lower. Cold-rolled sheet annealing is preferably maintained for 20 seconds or more in the above temperature range. Moreover, it is preferable that cold-rolled sheet annealing is hold | maintained for 1 minute or less within the said temperature range.
　表１のＮｏ．１－１～１－３に示す成分組成（残部はＦｅおよび不可避的不純物）を有するフェライト系ステンレス鋼を１００ｋｇ鋼塊に溶製した後、１０５０℃の温度に加熱して熱間圧延を行って板厚４．０ｍｍの熱延板を得た。 No. in Table 1. A ferritic stainless steel having the composition shown in 1-1 to 1-3 (the balance is Fe and inevitable impurities) is melted in a 100 kg steel ingot, heated to a temperature of 1050 ° C., and hot rolled. A hot-rolled sheet having a thickness of 4.0 mm was obtained.
　上述した各熱延板を５枚に分割し、その内の４枚を、大気中において、表１に示す８３０～１２００℃の各温度にて２０秒間焼鈍して熱延焼鈍板とし、表裏両面の研削を行ってスケールを除去して、冷間圧延用素材とした。
　また、各熱延板を分割した残り１枚は、大気雰囲気中において、８００℃で８時間焼鈍して熱延焼鈍板とし、表裏両面の研削を行ってスケールを除去して、冷間圧延用素材とした。 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 to form hot-rolled annealed sheets. Then, the scale was removed to obtain a material for cold rolling.
In addition, the remaining one sheet obtained by dividing each hot-rolled sheet is annealed at 800 ° C. for 8 hours in an air atmosphere to form a hot-rolled annealed sheet, and both the front and back surfaces are ground to remove the scales. The material.
　得られたそれぞれの冷間圧延用素材は、その後、冷間圧延で板厚：１．０ｍｍの冷延板とした。得られた冷延板に対して、大気雰囲気中において８００℃で２０秒間焼鈍し、冷延焼鈍板を得た。得られた冷延焼鈍板は、通常の方法で酸洗し、フェライト系ステンレス鋼冷延焼鈍酸洗板を得た。 Each obtained cold rolling material was then cold rolled into a cold rolled sheet having a thickness of 1.0 mm. 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.
　＜耐食性＞
　上記製造した冷延焼鈍酸洗板から、せん断加工により長さ８０ｍｍ×幅６０ｍｍの鋼板を切出した後、エメリー研磨紙で表面を６００番まで研磨し、水洗後、エタノール中にて５分間の超音波脱脂を行い試験片を得た。得られた試験片に対してＪＡＳＯ　Ｍ６０９－９１に準拠し腐食試験を実施し、耐食性を評価した。試験片は、端部と裏面をビニールテープで覆った後、長さ方向を縦にして、傾き：６０°で試験装置内へ設置した。１サイクルを塩水噴霧（５質量％ＮａＣｌ水溶液、３５℃）２ｈ→乾燥（６０℃、相対湿度４０％）４ｈ→湿潤（５０℃、相対湿度９５％以上）２ｈとし、３サイクル実施した。試験後、腐食面を外観撮影し、試験片中心の３０ｍｍ×３０ｍｍの領域について、得られた写真から画像解析にて銹面積率を算出した。銹面積率が２０％以下であったものを「○」（合格：優れている）、２０％超～３０％以下であったものを「□」（合格）、３０％よりも大きかったものを「▲」（不合格）と評価した。 <Corrosion resistance>
A steel plate having a length of 80 mm and a width of 60 mm is cut out from the cold-rolled annealed pickling plate produced above by grinding, then the surface is polished to No. 600 with emery polishing paper, washed with water, and in ethanol for over 5 minutes. Sonic degreasing was performed to obtain a test piece. 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).
　＜成形性＞
　さらに、上記製造した冷延焼鈍酸洗板から、ＪＩＳ　Ｚ　２２４１に規定される１３Ｂ号試験片を、圧延方向（Ｌ方向）、圧延方向に対して４５度方向（Ｄ方向）、および、圧延方向に対して直角方向（Ｃ方向）が試験片の長手となるようにそれぞれ採取し、同規格に準拠して常温で引張試験を行い、成形性を評価した。破断時全伸び（％）の三方向平均（（Ｌ＋２Ｄ＋Ｃ）／４、ただし、Ｌ、Ｄ、Ｃは各方向の破断伸び（％））が３２％以上であるものを「○」（合格：優れている）、３２％未満２８％以上であるものを「□」（合格）、２８％未満であるものを「▲」（不合格）とした。 <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. Three-directional average of total elongation at break (%) ((L + 2D + C) / 4, where L, D, and C are the break elongation (%) in each direction) of 32% or more, “Good” (Pass: Excellent) ), Less than 32% and 28% or more was designated as “□” (passed), and less than 28% was designated as “▲” (failed).
　＜耐リジング性＞
　さらに、上記製造した冷延焼鈍酸洗板から、ＪＩＳ　Ｚ　２２４１に規定される５号試験片を、圧延方向が試験片の長手となるように採取し、その表面を＃６００のエメリーペーパーを用いて研磨した後、引張試験を同規格に準拠して行い、２３％の引張ひずみを付与した。その後、その試験片の平行部中央の研磨面で圧延方向に直角の方向に、レーザー変位計を用いて表面形状を測定した。測定長は１ラインあたり１６ｍｍ、０．０５ｍｍ刻みで高さを測定した。また、ハイカットフィルター波長０．８ｍｍ、ローカットフィルター波長８ｍｍとしたＨａｎｎｉｎｇ窓関数型のＦＩＲ（Ｆｉｎｉｔｅ　Ｉｍｐｕｌｓｅ　Ｒｅｓｐｏｎｓｅ）バンドパスフィルターを用いて、平滑化およびうねり除去処理を行った。その後、処理を行った各ラインの形状データをもとに、各ラインの両端それぞれ２ｍｍ分のデータを排除して、ＪＩＳ　Ｂ　０６０１（２００１年）で規定される算術平均うねりＷａを各ラインにて測定した。なお、各ラインの間隔は０．１ｍｍとして、合計５０ライン測定した。そして、この算術平均うねりＷａの５０ラインの平均値を、鋼板表面のリジング高さとし、耐リジング性を評価した。
リジング高さが２．０μｍ以下の場合を「◇」（合格：特に優れている）、２．０μｍ超２．５μｍ以下の場合を「○」（合格：優れている）、２．５μｍ超３．０μｍ以下の場合を「□」（合格）、３．０μｍ超の場合を「▲」（不合格）とした。 <Ridging resistance>
Furthermore, from the manufactured cold-rolled annealed pickling plate, No. 5 test piece defined in JIS Z 2241 was collected so that the rolling direction was the length of the test piece, and the surface was used with # 600 emery paper. After polishing, a tensile test was performed according to the same standard, and a 23% tensile strain was applied. Thereafter, the surface shape was measured using a laser displacement meter in a direction perpendicular to the rolling direction on the polishing surface at the center of the parallel part of the test piece. The measurement length was 16 mm per line, and the height was measured in increments of 0.05 mm. In addition, 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. After that, based on the shape data of each processed line, 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 | undulation Wa was made into the ridging height of the steel plate surface, and ridging resistance was evaluated.
The case where the ridging height is 2.0 μm or less is “◇” (pass: excellent), the case where it is more than 2.0 μm and 2.5 μm or less is “◯” (pass: excellent), and more than 2.5 μm The case of 0.0 μm or less was designated as “□” (passed), and the case of more than 3.0 μm was designated as “▲” (failed).
　得られた結果を表１に示す。熱延板を９００℃以上１１００℃以下の温度範囲で５秒～１５分間保持した熱延板焼鈍を行った発明例は、いずれも耐食性の評価が「○」または「□」であり、かつ、成形性の評価が「○」であり、かつ、耐リジング性の評価が「◇」または「○」であり、耐食性に優れるとともに、成形性と耐リジング性に優れることが分かった。 The results obtained are shown in Table 1. The invention examples in which the hot-rolled sheet annealing was performed by holding the hot-rolled sheet in a temperature range of 900 ° C. or higher and 1100 ° C. or lower for 5 seconds to 15 minutes, both had a corrosion resistance evaluation of “◯” or “□”, and The evaluation of moldability was “◯” and the evaluation of ridging resistance was “◇” or “◯”, indicating that it was excellent in corrosion resistance and excellent in moldability and ridging resistance.
　いずれの成分組成を有する鋼においても、熱延板の焼鈍温度が９００℃未満の条件や熱延板の焼鈍温度が１１００℃超の条件の比較例においては、冷間圧延用素材に十分な面積率にてマルテンサイト相が含まれないため、冷間圧延によってコロニーが分断されず、耐リジング性が劣っていた。 In steels having any composition, in a comparative example where the annealing temperature of the hot-rolled sheet is less than 900 ° C. and the annealing temperature of the hot-rolled sheet is more than 1100 ° C., an area sufficient for the material for cold rolling Since the martensite phase was not included at a rate, colonies were not divided by cold rolling, and ridging resistance was poor.
Figure JPOXMLDOC01-appb-T000001
  
Figure JPOXMLDOC01-appb-T000001
  
　表２－１、表２－２のＮｏ．２－１～２－５７に示す成分組成を有する冷延焼鈍酸洗板を、実施例１に示した製造条件にて作製した。ただし、熱延板の焼鈍条件は、大気雰囲気中において、１０００℃で２０秒間焼鈍する条件とした。これらの冷延焼鈍酸洗板を、実施例１に示した各試験に供し、耐食性、成形性、および耐リジング性を評価した。 No. in Table 2-1 and Table 2-2. Cold-rolled annealed pickling plates having the component compositions shown in 2-1 to 2-57 were produced under the production conditions shown in Example 1. However, the annealing conditions for the hot-rolled sheet were the conditions for annealing at 1000 ° C. for 20 seconds in the air atmosphere. These cold-rolled annealed pickling plates were subjected to each test shown in Example 1, and corrosion resistance, formability, and ridging resistance were evaluated.
　得られた結果を表２－１、表２－２に示す。 The results obtained are shown in Tables 2-1 and 2-2.
Figure JPOXMLDOC01-appb-T000002
  
Figure JPOXMLDOC01-appb-T000002
  
   
　発明例は、耐食性の評価が「○」または「□」であり、かつ、成形性の評価が「○」または「□」であり、かつ、耐リジング性の評価が「◇」または「○」または「□」であり耐食性に優れるとともに、成形性と耐リジング性に優れることが分かった。 In the invention examples, the evaluation of corrosion resistance is “O” or “□”, the evaluation of moldability is “O” or “□”, and the evaluation of ridging resistance is “◇” or “O”. Alternatively, it was “□”, indicating excellent corrosion resistance and excellent moldability and ridging resistance.
　試験Ｎｏ．２－３５の比較例は、Ｃｒの含有量が本発明の成分範囲よりも低いため、耐食性が劣っていた。
　試験Ｎｏ．２－３６の比較例は、Ｃｒの含有量が本発明の成分範囲よりも高いため、耐リジング性が劣っていた。
　試験Ｎｏ．２－３７の比較例は、Ｎｉの含有量が本発明の成分範囲よりも低いため、耐食性が劣っていた。
　試験Ｎｏ．２－３８の比較例は、Ｎｉの含有量が本発明の成分範囲よりも高いため、成形性が劣っていた。
　試験Ｎｏ．２－３９、２－４１の比較例は、それぞれＣとＮとの含有量が本発明の成分範囲よりも低いため、耐リジング性が劣っていた。
　試験Ｎｏ．２－４０、２－４２の比較例は、それぞれＣとＮとの含有量が本発明の成分範囲よりも高いため、成形性が劣っていた。
　試験Ｎｏ．２－４３の比較例は、Ｓｉの含有量が本発明の成分範囲よりも高いため、成形性と耐リジング性が劣っていた。
　試験Ｎｏ．２－４４の比較例は、Ｃｒの含有量が本発明の成分範囲よりも高いため、耐リジング性が劣っていた。
　試験Ｎｏ．２－５２の比較例は、Ｔｉの含有量が本発明の成分範囲よりも高いため、耐リジング性が劣っていた。
　試験Ｎｏ．２－５３、２－５４、２－５６の比較例は、式（１）の値が０．０を超えているため、耐リジング性が劣っていた。
　試験Ｎｏ．２－５５の比較例は、Ｃｒの含有量が本発明の成分範囲よりも低く、さらに、式（１）の値が０．０を超えているため、耐食性と耐リジング性が劣っていた。
　試験Ｎｏ．２－５７の比較例は、Ｎｂの含有量が本発明の成分範囲よりも高いため、耐リジング性が劣っていた。 Test No. The Comparative Example 2-35 was inferior in corrosion resistance because the Cr content was lower than the component range of the present invention.
Test No. The comparative example 2-36 was inferior in ridging resistance because the Cr content was higher than the component range of the present invention.
Test No. The Comparative Example 2-37 was inferior in corrosion resistance because the Ni content was lower than the component range of the present invention.
Test No. The comparative example of 2-38 was inferior in moldability because the Ni content was higher than the component range of the present invention.
Test No. In Comparative Examples 2-39 and 2-41, the ridging resistance was inferior because the contents of C and N were lower than the component ranges of the present invention, respectively.
Test No. The comparative examples 2-40 and 2-42 were inferior in moldability because the contents of C and N were higher than the component range of the present invention.
Test No. The comparative example 2-43 was inferior in moldability and ridging resistance because the Si content was higher than the component range of the present invention.
Test No. The comparative example 2-44 was inferior in ridging resistance because the Cr content was higher than the component range of the present invention.
Test No. The comparative example 2-52 was inferior in ridging resistance because the Ti content was higher than the component range of the present invention.
Test No. The comparative examples of 2-53, 2-54, and 2-56 were inferior in ridging resistance because the value of the formula (1) exceeded 0.0.
Test No. In Comparative Example 2-55, the Cr content was lower than the component range of the present invention, and the value of formula (1) exceeded 0.0, so the corrosion resistance and ridging resistance were inferior.
Test No. In Comparative Example 2-57, the ridging resistance was inferior because the Nb content was higher than the component range of the present invention.
　本発明のフェライト系ステンレス鋼板は、耐食性に優れ、さらに成形性と耐リジング性に優れるので、家庭用調理器具をはじめとして、家電製品用部品、事務用品用部品、自動車内装用部品、自動車排気用配管、建材などの用途に対して好適に使用することができる。 The ferritic stainless steel sheet of the present invention is excellent in corrosion resistance, and further excellent in formability and ridging resistance. It can be suitably used for applications such as piping and building materials.

Claims (6)

  1. 　質量％で、
    Ｃ：０．００５～０．０３０％、
    Ｓｉ：０．０５～１．００％、
    Ｍｎ：０．０５～１．００％、
    Ｐ：０．０４０％以下、
    Ｓ：０．０３０％以下、
    Ａｌ：０．００１～０．１５０％、
    Ｃｒ：１０．８～１４．４％、
    Ｎｉ：０．０１～２．５０％、および
    Ｎ：０．００５～０．０６０％
    を含有し、残部がＦｅおよび不可避的不純物からなる成分組成を有し、
    破断伸びが２８％以上であり、圧延方向に２３％の引張歪みを付与した鋼板表面のリジング高さが３．０μｍ以下である、フェライト系ステンレス鋼板。     % By 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: 0.01-2.50%, and N: 0.005-0.060%
    And the balance has a component composition consisting of Fe and inevitable impurities,
    A ferritic stainless steel sheet having a breaking elongation of 28% or more and a ridging height of a steel sheet surface imparted with a tensile strain of 23% in the rolling direction is 3.0 μm or less.
  2. 　さらに、質量％で、
    Ｃｏ：０．０１～０．５０％、
    Ｃｕ：０．０１～０．８０％、
    Ｍｏ：０．０１～０．３０％、および
    Ｗ：０．０１～０．５０％
    のうちから選んだ１種または２種以上を含有する、請求項１に記載のフェライト系ステンレス鋼板。     Furthermore, in mass%,
    Co: 0.01 to 0.50%,
    Cu: 0.01 to 0.80%,
    Mo: 0.01 to 0.30% and W: 0.01 to 0.50%
    The ferritic stainless steel sheet according to claim 1, comprising one or more selected from among the above.
  3. 　さらに、質量％で、
    Ｔｉ：０．０１～０．３０％、
    Ｖ：０．０１～０．１０％、
    Ｚｒ：０．０１～０．１０％、および
    Ｎｂ：０．０１～０．３０％
    のうちから選んだ１種または２種以上を含有し、かつ、
    下記式（１）の値が０．０以下である、請求項１または２に記載のフェライト系ステンレス鋼板。
    ５４×（Ｔｉ＋Ｖ＋Ｚｒ＋Ｎｂ）－５×Ｍｎ－１９×Ｎｉ＋１．０　・・・式（１）
    ただし、上記式（１）における各元素記号は各元素の含有量（質量％）を表し、含有しない元素は０とする。     Furthermore, in mass%,
    Ti: 0.01 to 0.30%,
    V: 0.01 to 0.10%,
    Zr: 0.01 to 0.10%, and Nb: 0.01 to 0.30%
    Containing one or more selected from among, and
    The ferritic stainless steel sheet according to claim 1 or 2, wherein a value of the following formula (1) is 0.0 or less.
    54 × (Ti + V + Zr + Nb) −5 × Mn−19 × Ni + 1.0 Formula (1)
    However, each element symbol in the above formula (1) represents the content (% by mass) of each element, and the element not contained is 0.
  4. 　さらに、質量％で、
    Ｂ：０．０００３～０．００３０％、
    Ｍｇ：０．０００５～０．０１００％、
    Ｃａ：０．０００３～０．００３０％、
    Ｙ:０．０１～０．２０％、および
    ＲＥＭ（希土類金属）:０．００１～０．１００％
    のうちから選んだ１種または２種以上を含有する、請求項１～３のいずれかに記載のフェライト系ステンレス鋼板。     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%
    The ferritic stainless steel sheet according to any one of claims 1 to 3, comprising one or more selected from among the above.
  5. 　さらに、質量％で、
    Ｓｎ：０．００１～０．５００％、および
    Ｓｂ：０．００１～０．５００％
    のうちから選んだ１種または２種を含有する、請求項１～４のいずれかに記載のフェライト系ステンレス鋼板。     Furthermore, in mass%,
    Sn: 0.001 to 0.500%, and Sb: 0.001 to 0.500%
    The ferritic stainless steel sheet according to any one of claims 1 to 4, comprising one or two selected from among them.
  6. 　請求項１～５のいずれかに記載のフェライト系ステンレス鋼板の製造方法であって、
    前記成分組成を有する鋼スラブを熱間圧延し、熱延板とする工程と、
    前記熱延板を９００℃以上１１００℃以下の温度範囲で５秒～１５分間保持する熱延板焼鈍を行い、熱延焼鈍板とする工程と、
    前記熱延焼鈍板を冷間圧延し、冷延板とする工程と、
    前記冷延板を７８０℃以上８３０℃以下の温度範囲で５秒～５分間保持する冷延板焼鈍を行う工程と、
    を含む、フェライト系ステンレス鋼板の製造方法。     A method for producing a ferritic stainless steel sheet according to any one of claims 1 to 5,
    Hot-rolling a steel slab having the above-described composition to form a hot-rolled sheet;
    Performing the hot-rolled sheet annealing by holding the hot-rolled sheet in a temperature range of 900 ° C. or higher and 1100 ° C. or lower for 5 seconds to 15 minutes,
    Cold rolling the hot-rolled annealed plate to form a cold-rolled plate;
    Performing cold-rolled sheet annealing by 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;
    A method for producing a ferritic stainless steel sheet.
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