WO2014087648A1 - Tôle d'acier inoxydable ferritique - Google Patents

Tôle d'acier inoxydable ferritique Download PDF

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Publication number
WO2014087648A1
WO2014087648A1 PCT/JP2013/007124 JP2013007124W WO2014087648A1 WO 2014087648 A1 WO2014087648 A1 WO 2014087648A1 JP 2013007124 W JP2013007124 W JP 2013007124W WO 2014087648 A1 WO2014087648 A1 WO 2014087648A1
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amount
stainless steel
steel sheet
range
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PCT/JP2013/007124
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Japanese (ja)
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正崇 吉野
太田　裕樹
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Ｊｆｅスチール株式会社
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Priority to CN201380051013.5A priority Critical patent/CN104685089B/zh
Priority to IN1886DEN2015 priority patent/IN2015DN01886A/en
Priority to KR1020157006722A priority patent/KR101705135B1/ko
Priority to MYPI2015701001A priority patent/MY182247A/en
Priority to JP2014519731A priority patent/JP5664826B2/ja
Publication of WO2014087648A1 publication Critical patent/WO2014087648A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • the present invention relates to a ferritic stainless steel sheet, and particularly to a ferritic stainless steel sheet having excellent surface properties.
  • Stainless steel sheets are roughly classified into ferritic stainless steel sheets represented by SUS430 and austenitic stainless steel sheets represented by SUS304.
  • Ferritic stainless steel sheets have a smaller thermal expansion coefficient and higher thermal conductivity than austenitic stainless steel sheets. For this reason, the ferritic stainless steel sheet is excellent in thermal fatigue characteristics. In addition, stress corrosion cracking resistance is less likely to occur.
  • Ferritic stainless steel sheets with these properties are used in automotive exhaust systems that require excellent thermal fatigue properties in addition to heat resistance and oxidation resistance, and excellent stress corrosion cracking resistance. It is applied to kitchen facilities and electric water heaters that require high power.
  • ferritic stainless steel sheets have the great advantage that they can be manufactured at a low cost because they contain less expensive elements such as Ni and Mn, which are austenite-forming elements. Have. These excellent properties have been evaluated, and ferritic stainless steel sheets have been applied to various applications, and their needs have been increasing in recent years.
  • the ferritic stainless steel sheet applied for such applications is required to have not only the above properties but also excellent surface properties.
  • Patent Document 1 discloses a technique for reducing the generation of TiN inclusions by regulating the amounts of Ti, N, and O.
  • Patent Document 1 discloses a technique for reducing the generation of TiN inclusions by regulating the amounts of Ti, N, and O.
  • the surface texture may deteriorate, and an excellent surface texture cannot be obtained only by component regulation considering only oxides and nitrides.
  • the present invention has been made to solve the above-described problems, and an object thereof is to provide a ferritic stainless steel sheet having excellent surface properties.
  • the present inventors investigated the types of inclusions generated in the ferritic stainless steel sheet and the amount of the inclusions.
  • coarse Ti-based sulfides and Ti-based phosphides Ti-based oxides.
  • Phosphide was also produced, and it was revealed that this coarse Ti-based sulfide and phosphide deteriorated the surface properties of the steel sheet.
  • the present inventors then studied diligently about the steel plate component range in which the surface properties do not deteriorate due to Ti-based oxides, sulfides and phosphides. As a result, it has been found that by appropriately managing the amounts of Ti, S, P, and O, the formation of the inclusions can be suppressed, and the surface properties of the steel sheet are greatly improved.
  • the present invention has been made based on the above findings, and the gist thereof is as follows. [1] By mass%, C: 0.004% to 0.014%, N: 0.004% to 0.014%, Si: 0.01% to 0.30%, Mn: 0.00.
  • a ferritic stainless steel sheet having excellent surface properties can be obtained.
  • the present invention provides a technology for obtaining a ferritic stainless steel sheet having excellent surface properties by effectively suppressing the formation of Ti-based sulfides and phosphides, which have not been considered in the past, in addition to Ti-based oxides.
  • Ti-based sulfides and phosphides which have not been considered in the past, in addition to Ti-based oxides.
  • regulated the component composition of the steel plate of this invention below is demonstrated.
  • all the component% means the mass% unless there is particular notice.
  • C 0.004% or more and 0.014% or less
  • the amount of C exceeds 0.014%, the workability is deteriorated and the corrosion resistance of the welded part is significantly lowered when welding is performed.
  • a lower C content is preferable from the viewpoint of corrosion resistance and workability.
  • the C content is in the range of 0.004% to 0.014%.
  • it is 0.004% or more and 0.011% or less of range. More preferably, it is 0.005% or more and 0.008% or less of range.
  • the N amount is set in the range of 0.004% to 0.014%.
  • the N amount is set in the range of 0.004% or more and 0.011% or less of range. More preferably, it is 0.006% or more and 0.009% or less of range.
  • Si 0.01% or more and 0.30% or less Si is an element useful as a deoxidizer in the steelmaking process. This effect can be obtained by making the Si amount 0.01% or more. The effect increases as the Si amount increases. However, if the amount of Si exceeds 0.30%, the rolling load in the hot rolling process increases and the productivity decreases, and a large amount of oxide scale is generated on the surface, resulting in an increase in surface defects. Therefore, it is not preferable. Therefore, the Si amount is set to 0.01% or more and 0.30% or less. In order to perform descaling more easily in the annealing / pickling process, the Si content is preferably 0.25% or less. More preferably, it is 0.20% or less.
  • Mn 0.01% or more and 0.30% or less Mn has an effect of increasing the strength of the steel sheet, and is also an element useful as a deoxidizer. In order to acquire these effects, it is necessary to make Mn amount 0.01% or more. However, if the amount of Mn exceeds 0.30%, the thickness of the oxide scale generated in the annealing process of the hot-rolled sheet or the annealing process of the cold-rolled sheet becomes thick, and the surface properties are lowered. Therefore, the amount of Mn is 0.01% or more and 0.30% or less. Preferably it is 0.05 to 0.25% of range. More preferably, it is 0.05 to 0.20% of range.
  • P 0.025% or more and 0.040% or less
  • P is an element inevitably contained in the steel sheet. Further, excessive P content reduces weldability and easily causes intergranular corrosion. This tendency becomes remarkable when the amount of P exceeds 0.040%. A lower P content is preferable from the viewpoint of weldability and prevention of intergranular corrosion.
  • the P content is in the range of 0.025% to 0.040%. Preferably, it is 0.025% or more and 0.035% or less. More preferably, it is 0.025% or more and 0.030% or less.
  • S 0.010% or less S, like P, is an element inevitably contained in the steel sheet.
  • the S amount is 0.010% or less.
  • it is 0.007% or less. More preferably, it is 0.004% or less.
  • Al 0.01% or more and 0.08% or less
  • Al is an effective deoxidizer. This effect as a deoxidizer can be obtained by making the Al content 0.01% or more. However, if the amount of Al exceeds 0.08%, surface defects due to Al-based inclusions may occur, and pickling properties in the annealing process are deteriorated, which is not preferable in production. Therefore, the Al content is set in a range of 0.01% to 0.08%. Preferably it is 0.01% or more and 0.06% or less of range. More preferably, it is 0.02% or more and 0.05% or less.
  • the Cr content is in the range of 10.5% or more and 24.0% or less.
  • the Cr content is 12.0% or more and 24.0% or less of range. More preferably, it is 15.0% or more and 21.5% or less of range. Even more preferably, it is in the range of 16.0% or more and 19.0% or less.
  • Ni 0.01% or more and 0.40% or less
  • Ni is an element that improves the corrosion resistance of a stainless steel plate, and the progress of corrosion in a corrosive environment where a passive film cannot be formed and active dissolution occurs. It is an element which suppresses. This effect is obtained by setting the Ni content to 0.01% or more, and increases as the Ni content increases. However, when the Ni content exceeds 0.40%, workability is lowered and stress corrosion cracking is likely to occur. Furthermore, since Ni is an expensive element, an increase in the amount of Ni causes an increase in manufacturing cost, which is not preferable. Therefore, the Ni content is 0.01% or more and 0.40% or less. Preferably it is 0.05 to 0.30% of range. More preferably, it is 0.10% or more and 0.20% or less of range.
  • Ti 0.20% or more and 0.38% or less Ti combines with C or N to improve workability or prevent the weld from becoming sensitized and improve the corrosion resistance of the weld. In order to obtain this effect, the Ti amount needs to be 0.20% or more. However, if the amount of Ti exceeds 0.38%, coarse Ti carbonitride is generated in the casting process and causes surface defects, which is not preferable. Therefore, the Ti amount is set to 0.20% or more and 0.38% or less. Preferably it is 0.20% or more and 0.35% or less of range. More preferably, it is 0.25% or more and 0.35% or less of range.
  • Nb 0.012% or less If the Nb content exceeds 0.012%, the recrystallization temperature rises, and good mechanical properties are achieved unless the annealing temperature of the hot-rolled sheet or the annealing temperature of the cold-rolled sheet is increased. Cannot be obtained. When these annealing temperatures are raised, the scale generated during annealing becomes thicker. Therefore, some scales remain after pickling, or the surface is roughened by performing strong pickling to remove thick scales, and the surface properties are deteriorated. Therefore, the Nb content is 0.012% or less. Preferably it is 0.008% or less. More preferably, it is 0.005% or less.
  • O 0.0060% or less
  • O is an element that improves the penetration depth during welding. However, if the amount of O exceeds 0.0060%, the amount of oxide inclusions increases and the corrosion resistance decreases. Therefore, the O amount is set to 0.0060% or less. Preferably it is 0.0045% or less. More preferably, it is 0.0030% or less.
  • (P% + S% + 10 ⁇ O%) ⁇ Ti% ⁇ 0.025 Ti forms inclusions with P, S and O.
  • (P% + S% + 10 ⁇ O%) ⁇ Ti% exceeds 0.025 the amount of Ti-based inclusions generated on the steel sheet surface increases and the inclusions become coarse, resulting in a decrease in surface defects and surface gloss. Since surface quality deteriorates, it is not preferable. Further, if (P% + S% + 10 ⁇ O%) ⁇ Ti% exceeds 0.025, it is preferable because coarse Ti-based inclusions generated on the surface of the steel sheet cause defects in the passive film and decrease the corrosion resistance. Absent. Therefore, (P% + S% + 10 ⁇ O%) ⁇ Ti% is set to 0.025 or less. P%, S%, 0%, and Ti% represent the contents (mass%) of P, S, O, and Ti, respectively.
  • the ferritic stainless steel sheet of the present invention contains the above-mentioned essential components, and the balance consists of Fe and inevitable impurities.
  • ferritic stainless steel sheet of the present invention is further optionally selected from one or more selected from Cu, Mo and V, and from Zr, REM, W, Co, B, Mg and Ca. 1 type (s) or 2 or more types selected can be contained within the following range.
  • Cu is an element that improves corrosion resistance.
  • Cu is an element particularly effective for improving the corrosion resistance of the base material and the weld when the steel plate is in an aqueous solution or when weakly acidic water droplets adhere to the steel plate. This effect is obtained by making Cu 0.01% or more, and the effect becomes higher as the amount of Cu increases.
  • the amount of Cu exceeds 0.48%, hot workability is deteriorated, and an oxide derived from Cu called red scale is formed on the slab during hot rolling, resulting in surface defects. Therefore, it is not preferable.
  • the amount of Cu shall be 0.01% or more and 0.48% or less.
  • it is 0.10% or more and 0.48% or less of range. More preferably, it is 0.30% or more and 0.45% or less of range.
  • Mo 0.01% or more and 1.20% or less
  • Mo is an element that remarkably improves the corrosion resistance of the stainless steel plate. This effect is obtained by setting the Mo amount to 0.01% or more, and the effect increases as the Mo amount increases. However, if the Mo content exceeds 1.20%, the hot workability is deteriorated and surface defects frequently occur during hot rolling. Moreover, since Mo is an expensive element, the addition of a large amount increases the manufacturing cost. Therefore, when adding Mo, the amount of Mo shall be 0.01% or more and 1.20% or less. Preferably it is 0.30% or more and 1.20% or less of range. More preferably, it is 0.30% or more and 0.90% or less of range. More preferably, it is 0.40% or more and 0.60% or less of range.
  • V 0.01% or more and 0.10% or less
  • V is an element effective for refining crystal grains after annealing, preventing surface deteorations and improving fatigue characteristics. Further, V is combined with C or N and has an effect of suppressing a decrease in corrosion resistance due to the sensitization of the welded portion. These effects can be obtained by making the V amount 0.01% or more. However, if the V amount exceeds 0.10%, the workability is lowered and the raw material cost is increased, which is not preferable. Therefore, when adding V, the amount of V is made 0.01% or more and 0.10% or less. Preferably it is 0.01% or more and 0.07% or less of range. More preferably, it is 0.02% or more and 0.05% or less.
  • Zr combines with C and N to sensitize welds Has the effect of increasing the high temperature strength. These effects can be obtained by making the amount of Zr 0.01% or more. On the other hand, if the amount of Zr exceeds 0.20%, workability deteriorates. Moreover, since Zr is an expensive element, excessive addition causes an increase in manufacturing cost, which is not preferable. Therefore, when adding Zr, the amount of Zr shall be 0.01% or more and 0.20% or less. Preferably, the range is 0.01% or more and 0.10% or less.
  • REM 0.001% or more and 0.100% or less REM has the effect of improving oxidation resistance, and in particular, suppresses the formation of an oxide film on the weld and improves the corrosion resistance of the weld. effective.
  • the REM amount needs to be 0.001% or more.
  • the amount of REM shall be 0.001% or more and 0.100% or less.
  • it is set as 0.001% or more and 0.050% or less of range.
  • W 0.01% or more and 0.20% or less W, like Mo, has the effect of improving the corrosion resistance. This effect can be obtained by making the W amount 0.01% or more.
  • the amount of W exceeds 0.20%, the strength increases, and the productivity is lowered due to an increase in rolling load or the like, which is not preferable.
  • the W content is in the range of 0.01% to 0.20%.
  • the range is 0.01% or more and 0.10% or less.
  • Co 0.01% or more and 0.20% or less
  • Co is an element that improves toughness. This effect can be obtained by making the Co content 0.01% or more.
  • the amount of Co exceeds 0.20%, workability deteriorates. Therefore, when adding Co, the amount of Co is set to a range of 0.01% or more and 0.20% or less. Preferably, the range is 0.01% or more and 0.10% or less.
  • B 0.0002% or more and 0.0020% or less B is an element effective for improving resistance to secondary working embrittlement after deep drawing. This effect can be obtained by making the B amount 0.0002% or more. On the other hand, if the amount of B exceeds 0.0020%, the rolling load during hot rolling increases and surface defects increase, which is not preferable. Therefore, when adding B, the amount of B is made into the range of 0.0002% or more and 0.0020% or less. Preferably it is 0.0005% or more and 0.0015% or less of range.
  • Mg 0.0002% or more and 0.0010% or less
  • Mg is an element that improves the rate of equiaxed crystals of the slab and is effective in improving workability and toughness. Furthermore, in a steel sheet containing Ti as in the present invention, the toughness decreases when the Ti carbonitride becomes coarse, but Mg also has an effect of suppressing the coarsening of the Ti carbonitride. These effects can be obtained by setting the Mg amount to 0.0002% or more. On the other hand, if the amount of Mg exceeds 0.0010%, the amount of Mg inclusions increases and the surface properties of the steel sheet are deteriorated. Therefore, when adding Mg, the amount of Mg is set in the range of 0.0002% to 0.0010%. Preferably it is 0.0002% or more and 0.0004% or less of range.
  • Ca 0.0005% or more and 0.0030% or less
  • Ca is an effective component for preventing the choke of nozzle due to precipitation of Ti inclusions which are likely to occur during continuous casting. The effect is acquired by making Ca amount 0.0005% or more. However, if the Ca content exceeds 0.0030%, the corrosion resistance decreases due to the formation of CaS. Therefore, when Ca is added, the Ca content is in the range of 0.0005% to 0.0030%. Preferably it is 0.0005% or more and 0.0020% or less of range. More preferably, it is 0.0005% or more and 0.0015% or less of range.
  • the ferritic stainless steel sheet of the present invention is obtained by melting a molten steel having the above composition by a known method such as a converter, an electric furnace, a vacuum melting furnace or the like, and continuously casting or ingot-and-bloomig method.
  • Steel material (slab). The slab is heated at 1100 to 1250 ° C. for 1 to 24 hours, or directly hot-rolled as cast without heating to form a hot-rolled sheet.
  • hot-rolled sheets are subjected to continuous annealing at 800 to 1100 ° C. and batch-annealing hot-rolled sheets at 700 to 900 ° C.
  • the hot-rolled sheet after annealing or the unrolled hot-rolled sheet is subjected to pickling and cold rolling to become a cold-rolled sheet.
  • the cold-rolled sheet is annealed and pickled to become a product.
  • Cold rolling is preferably performed at a rolling reduction of 50% or more from the viewpoints of ductility, bendability, press formability, and leveling.
  • the recrystallization annealing of cold-rolled sheets is generally performed according to JIS G 0203 surface finish, No. In the case of a 2B finished product, it is preferable to carry out at 800 to 1000 ° C. in view of obtaining good mechanical properties and pickling properties. In order to obtain more gloss, BA annealing (bright annealing) may be performed.
  • grinding or polishing may be performed.
  • a stainless steel plate having the chemical composition shown in Table 1 (the essential components are shown in Table 1-1 and the optional components are shown in Table 1-2) was melted in a 50 kg small vacuum melting furnace. These steel ingots were heated to 1150 ° C. and then hot-rolled to obtain 3.5 mm thick hot rolled sheets. Subsequently, the hot-rolled sheet obtained above was annealed at 950 ° C. for 10 minutes, then shot blasted, pickled with a mixed acid of hydrofluoric acid and nitric acid, and cold-rolled to a thickness of 0.8 mm. Cold-rolled sheet was used. The obtained cold-rolled sheet was subjected to finish annealing at 900 ° C. in an air atmosphere, and then pickled with a mixed acid of hydrofluoric acid and nitric acid.
  • salt spray cycle test The corrosion resistance of the cold-rolled annealed pickling plates obtained as described above was evaluated by visual inspection and a salt spray cycle test.
  • salt spray (5% NaCl, 35 ° C., spray 2 h) ⁇ dry (60 ° C., 4 h, relative humidity 40%) ⁇ wet (50 ° C., 2 h, relative humidity ⁇ 95%) is one cycle. Five cycles were performed.
  • Table 2 shows the results obtained as described above.
  • Comparative Example B1 in which the Cr content is less than the range of the present invention although the predetermined surface quality was obtained, corrosion occurred on the entire surface of the test piece in the salt spray cycle test, and sufficient corrosion resistance was not obtained.
  • Comparative Example B2 in which Cr was added beyond the scope of the present invention was not tested because the hot-rolled sheet was poor in toughness and cracks occurred in the next cold rolling process.
  • ferritic stainless steel plate obtained by the present invention has excellent surface quality, it is suitable for use in automobile parts such as building materials and molding materials.

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Abstract

La présente invention concerne une tôle d'acier inoxydable ferritique. Une tôle d'acier inoxydable ferritique caractérisée en ce qu'elle contient, en pourcentage en masse, au moins 0,004 % mais au plus 0,014 % de C, au moins 0,004 % mais au plus 0,014 % de N, au moins 0,01 % mais au plus 0,30 % de Si, au moins 0,01 % mais au plus 0,30 % de Mn, au moins 0,025 % mais au plus 0,040 % de P, au plus 0,010 % de S, au moins 0,01 % mais au plus 0,08 % d'Al, au moins 10,5 % mais au plus 24,0 % de Cr, au moins 0,01 % mais au plus 0,40 % de Ni, au moins 0,20 % mais au plus 0,38 % de Ti, au plus 0,012 % de Nb et au plus 0,0060 % d'O, et les teneurs en P, S, O et Ti sont telles qu'elles satisfont à la relation (%P + %S + 10 × %O) × %T% ≤ 0,025, le complément étant du Fe et les impuretés inévitables. Dans cette relation, %P, %S, %O et %Ti représentent respectivement les teneurs (en pourcentage en masse) de P, S, O et Ti.
PCT/JP2013/007124 2012-12-07 2013-12-04 Tôle d'acier inoxydable ferritique WO2014087648A1 (fr)

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CN201380051013.5A CN104685089B (zh) 2012-12-07 2013-12-04 铁素体系不锈钢板
IN1886DEN2015 IN2015DN01886A (fr) 2012-12-07 2013-12-04
KR1020157006722A KR101705135B1 (ko) 2012-12-07 2013-12-04 페라이트계 스테인리스 강판
MYPI2015701001A MY182247A (en) 2012-12-07 2013-12-04 Ferritic stainless steel sheet
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EP3438310A4 (fr) * 2016-03-29 2019-02-06 JFE Steel Corporation Tôle d'acier inoxydable ferritique
JP2020164924A (ja) * 2019-03-29 2020-10-08 日鉄ステンレス株式会社 高純度フェライト系ステンレス鋼及び高純度フェライト系ステンレス鋼鋳片
US11261512B2 (en) 2016-09-02 2022-03-01 Jfe Steel Corporation Ferritic stainless steel
US11326236B2 (en) * 2017-02-23 2022-05-10 Nippon Steel Stainless Steel Corporation Black ferrite-based stainless steel sheet
US11365467B2 (en) 2017-05-26 2022-06-21 Jfe Steel Corporation Ferritic stainless steel

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US20180171430A1 (en) * 2015-07-02 2018-06-21 Jfe Steel Corporation Ferritic stainless steel sheet and method for manufacturing the same
ES2727177T3 (es) * 2015-09-30 2019-10-14 Jfe Steel Corp Chapa de acero inoxidable ferrítico
CN108411198A (zh) * 2018-03-28 2018-08-17 浙江益宏不锈钢有限公司 一种高性能不锈钢无缝钢管及其制造方法
KR20230018458A (ko) * 2020-06-02 2023-02-07 닛테츠 스테인레스 가부시키가이샤 페라이트계 스테인리스강

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EP3438310A4 (fr) * 2016-03-29 2019-02-06 JFE Steel Corporation Tôle d'acier inoxydable ferritique
US20190106775A1 (en) * 2016-03-29 2019-04-11 Jfe Steel Corporation Ferritic stainless steel sheet
US11261512B2 (en) 2016-09-02 2022-03-01 Jfe Steel Corporation Ferritic stainless steel
US11326236B2 (en) * 2017-02-23 2022-05-10 Nippon Steel Stainless Steel Corporation Black ferrite-based stainless steel sheet
US11365467B2 (en) 2017-05-26 2022-06-21 Jfe Steel Corporation Ferritic stainless steel
JP2020164924A (ja) * 2019-03-29 2020-10-08 日鉄ステンレス株式会社 高純度フェライト系ステンレス鋼及び高純度フェライト系ステンレス鋼鋳片
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CN104685089A (zh) 2015-06-03
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JPWO2014087648A1 (ja) 2017-01-05
KR101705135B1 (ko) 2017-02-09
TW201435096A (zh) 2014-09-16
KR20150038680A (ko) 2015-04-08
IN2015DN01886A (fr) 2015-08-07
CN104685089B (zh) 2016-08-17
JP5664826B2 (ja) 2015-02-04

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