EP3318654B1 - Tôle d'acier inoxydable ferritique - Google Patents

Tôle d'acier inoxydable ferritique Download PDF

Info

Publication number
EP3318654B1
EP3318654B1 EP16850651.7A EP16850651A EP3318654B1 EP 3318654 B1 EP3318654 B1 EP 3318654B1 EP 16850651 A EP16850651 A EP 16850651A EP 3318654 B1 EP3318654 B1 EP 3318654B1
Authority
EP
European Patent Office
Prior art keywords
content
case
steel sheet
comparative example
less
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP16850651.7A
Other languages
German (de)
English (en)
Other versions
EP3318654A1 (fr
EP3318654A4 (fr
Inventor
Shuji Nishida
Tomohiro Ishii
Mitsuyuki Fujisawa
Chikara Kami
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP3318654A1 publication Critical patent/EP3318654A1/fr
Publication of EP3318654A4 publication Critical patent/EP3318654A4/fr
Application granted granted Critical
Publication of EP3318654B1 publication Critical patent/EP3318654B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • 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
    • C22C38/001—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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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

Definitions

  • the present invention relates to a ferritic stainless steel sheet having excellent corrosion resistance, only a small quantity of surface defects, and excellent toughness.
  • a ferritic stainless steel sheet which does not contain Ni in a large amount, is a material having a lower price and more excellent price stability than those of an austenitic stainless steel sheet.
  • ferritic stainless steel sheets are used in various applications such as building materials, transport machine, home electrical appliances, and kitchen appliances, since they are excellent in terms of rust resistance.
  • the kind of ferritic stainless steel sheet which is used particularly in a harsh corrosive environment is a SUS443J1-type stainless steel sheet (JIS G 4305), which has excellent corrosion resistance equivalent to that of a SUS304-type stainless steel sheet (JIS G 4305, 18-mass%-Cr-8-mass%-Ni-based), which is an austenitic stainless steel, as a result of containing 20.0 mass% to 23.0 mass% of Cr, 0.3 mass% to 0.8 mass% of Cu, and sufficient amounts of stabilizing chemical elements (Ti, Nb, and Zr).
  • SUS443J1-type stainless steel which is commonly used is SUS443J1-type stainless steel containing mainly Ti as a stabilizing chemical element.
  • Such steel is excellent in terms of workability because texture growth is promoted as a result of containing Ti.
  • it is possible to manufacture such steel by using a cold-rolled-sheet annealing and pickling line which is used for common steel, which results in high productivity.
  • streaks surface defects
  • Patent Literature 1 and Patent Literature 2 describe the prevention of surface defects and the improvement of toughness regarding Ti-containing ferritic stainless steel.
  • Patent Literature 1 discloses a method for manufacturing Ti-containing ferritic stainless steel having excellent roping resistance and good surface quality.
  • the surface defect of a cold-rolled and annealed steel sheet is prevented by controlling the solidifying temperature of the steel, casting temperature, and TiN-precipitating temperature in the steel so that a specified relationship is satisfied in order to control the precipitation of TiN when the molten steel is cast.
  • Patent Literature 2 discloses a ferritic stainless steel sheet which has excellent toughness and good corrosion resistance and which is excellent in terms of productivity and economic efficiency and a method for manufacturing the steel sheet.
  • the toughness of a hot-rolled and annealed steel sheet and the toughness of a cold-rolled and annealed steel sheet are improved by allowing nitrides in the steel to exist in the form of ZrN.
  • WO 2008/082096 A1 discloses a high chromium ferritic stainless steel with excellent corrosion resistance and excellent discoloration resistance.
  • An object of the present invention is to provide a ferritic stainless steel sheet excellent in corrosion resistance in which a decrease in the quantity of surface defects and an improvement in toughness are realized at the same time and which is sufficiently softened even in the case where cold-rolled-sheet annealing is performed at a temperature equivalent to that for conventional Ti-containing SUS443J1-type stainless steel.
  • the present inventors in response to the problems described above, conducted comprehensive investigations in order to realize a decrease in the quantity of surface defects and an improvement in toughness at the same time and, as a result, found that it is possible to improve the toughness of Ti-containing SUS443J1-type stainless steel by adding appropriate amounts of Zr and Nb in combination to Ti-containing SUS443J1-type stainless steel in order to change the precipitation form of TiN, which causes a deterioration in toughness, without an increase in cold-rolled-sheet annealing temperature. Moreover, it was found that, since it is possible to precipitate Ti-based inclusions in a finely dispersed form by this effect, it is possible to decrease the quantity of surface defects of a steel sheet caused by TiN.
  • the stabilizing chemical elements Ti, Nb, and Zr
  • the content of Ti which is the main stabilizing chemical element
  • the Nb content which is equal to or less than the Ti content
  • the Zr content which is equal to or less than the Nb content
  • the mechanism of these is supposed to be as follows.
  • the present invention is based on the findings described above, and the subject matter of the present invention is as follows.
  • the C is a chemical element which is effective for improving the strength of steel. Such an effect is obtained in the case where the C content is 0.001% or more. However, in the case where the C content is more than 0.020%, there is a significant deterioration in corrosion resistance and workability. Therefore, the C content is set to be 0.020% or less, preferably 0.015% or less, or more preferably 0.010% or less.
  • Si is a chemical element which is effective as a deoxidizing agent. Such an effect is obtained in the case where the Si content is 0.05% or more.
  • the Si content is more than 0.40%, there is a deterioration in workability due to an increase in the hardness of steel.
  • the Si content is more than 0.40%, since there is a decrease in the amount of scale formed on the upper surface of a slab, which has a lubrication effect when hot rolling is performed, there is an increase in the quantity of surface defects. Therefore, the Si content is limited to be in the range of 0.05% to 0.15%. It is more preferable that the lower limit of the Si content be 0.08% or more.
  • Mn has a deoxidizing function. Such an effect of Mn is obtained in the case where the Mn content is 0.05% or more.
  • the Mn content is more than 1.00%, since the precipitation and coarsening of MnS are promoted, there is a deterioration in corrosion resistance. Therefore, the Mn content is limited to be in the range of 0.05% to 1.00%. It is preferable that the lower limit of the Mn content be 0.10% or more, or more preferably 0.15% or more. It is preferable that the upper limit of the Mn content be less than 0.30%, or more preferably 0.25% or less.
  • P is a chemical element which deteriorates corrosion resistance.
  • the P content is set to be 0.040% or less, or preferably 0.030% or less.
  • the S content be smaller, and the S content is set to be 0.030% or less, or preferably 0.020% or less.
  • Al is a chemical element which is effective for deoxidation. Such an effect is obtained in the case where the Al content is 0.001% or more.
  • the Al content is more than 0.15%, since there is a decrease in the amount of scale formed on the surface of a slab, which has a lubrication effect when hot rolling is performed, there is an increase in the quantity of surface defects. Therefore, the Al content is limited to be in the range of 0.001% to 0.15%. It is preferable that the lower limit of the Al content be 0.005% or more, or more preferably 0.01% or more. It is preferable that the upper limit of the Al content be 0.10% or less, or more preferably 0.05% or less.
  • the Cr is a chemical element which improves corrosion resistance by forming a passive film on the surface. It is not possible to achieve sufficient corrosion resistance in the case where the Cr content is less than 20.0%. On the other hand, in the case where the Cr content is more than 23.0%, there is a tendency for toughness to deteriorate due to a ⁇ phase and 475°C embrittlement. Therefore, the Cr content is set to be 20.0% to 23.0%. It is preferable the lower limit of the Cr content be 20.5% or more. It is preferable that the upper limit of the Cr content be 22.0% or less, or more preferably 21.5% or less.
  • Ni is a chemical element which makes it possible to maintain a passive state even at a lower pH by inhibiting an anode reaction due to acid. That is, Ni improves corrosion resistance by markedly inhibiting the progress of corrosion in an active dissolution state as a result of increasing the effect of crevice corrosion resistance. Such an effect of Ni is obtained in the case where the Ni content is 0.01% or more. On the other hand, in the case where the Ni content is more than 0.80%, there is a deterioration in workability due to an increase in the hardness of steel. Therefore, the Ni content is limited to be 0.01% to 0.80%. It is preferable that the lower limit of the Ni content be 0.05% or more, or more preferably 0.10% or more. It is preferable that the upper limit of the Ni content be 0.40% or less, or more preferably 0.25% or less.
  • the Cu is a chemical element which improves corrosion resistance by strengthening a passive film.
  • the Cu content is set to be 0.30% to 0.80%. It is preferable that the lower limit of the Cu content be 0.35% or more, or more preferably 0.40% or more. It is preferable that the upper limit of the Cu content be 0.60% or less, or more preferably 0.45% or less.
  • Ti is a chemical element which improves corrosion resistance by preventing sensitization due to Cr carbonitrides as a result of fixing C and N.
  • TiN which is formed as a result of containing Ti, causes a deterioration in toughness.
  • the above-mentioned deterioration in toughness due to Ti is suppressed by the combination effect of Nb and Zr as described below.
  • the effect of improving corrosion resistance through the use of Ti is obtained in the case where the Ti content is 0.10% or more.
  • the Ti content is more than 0.50%, there is a deterioration in workability due to an increase in the hardness of a stainless steel sheet.
  • the Ti content is set to be in the range of 0.10% to 0.50%. It is preferable that the lower limit of the Ti content be 0.15% or more, or more preferably 0.18% or more. It is preferable that the upper limit of the Ti content be 0.35% or less, or more preferably 0.26% or less.
  • Nb 0.010% to 0.150%
  • Nb is, like Ti, a chemical element which improves corrosion resistance by preventing sensitization due to Cr carbonitrides as a result of fixing C and N. Moreover, Nb improves toughness and inhibits a surface defect from occurring by the combination effect with Zr described below. Such effects are obtained in the case where the Nb content is 0.010% or more. On the other hand, in the case where the Nb content is more than 0.150%, there is a deterioration in workability due to an increase in the hardness of a stainless steel sheet. In addition, in the case where the Nb content is more than 0.150%, since there is an increase in recrystallization temperature, there is a deterioration in manufacturability.
  • the Nb content is set to be in the range of 0.010% to 0.150%. It is preferable that the lower limit of the Nb content be 0.030% or more, or more preferably 0.070% or more. It is preferable that the upper limit of the Nb content be less than 0.100%, or more preferably 0.090% or less.
  • Zr is, like Ti, a chemical element which improves corrosion resistance by preventing sensitization due to Cr carbonitrides as a result of fixing C and N. Moreover, Zr improves toughness and inhibits a surface defect from occurring by the combination effect with Nb described below. It is necessary that the Zr content be 0.005% or more in order to obtained such effects. On the other hand, in the case where the Zr content is more than 0.150%, since Zr-based inclusions are precipitated on the surface, there is an increase in the quantity of surface defects. Therefore, the Zr content is limited to be in the range of 0.005% to 0.150%. It is preferable that the lower limit of the Zr content be 0.010% or more, or more preferably 0.030% or more. It is preferable that the upper limit of the Zr content be less than 0.100%, or more preferably 0.080% or less.
  • the stabilizing chemical elements Ti, Nb, and Zr
  • the chemical composition of a SUS443J1-type stainless steel so that the Ti content is 0.10% to 0.50%, the Nb content is 0.010% to 0.150%, and the Zr content is 0.005% to 0.150% under the condition expressed by relational expression (1) below, it is possible to allow sufficient softening to occur by performing cold-rolled-sheet annealing even at a temperature equivalent to that for the case where a stabilizing chemical element is limited to Ti, and it is possible to realize a decrease in the quantity of surface defects and a high toughness at the same time.
  • the mechanism of these is supposed to be as follows.
  • each of Zr, Nb, and Ti in relational expression (1) denotes the content (mass%) of the corresponding chemical element.
  • Ti and Nb it is preferable that the relational expression Ti ⁇ 1.5Nb, or more preferably Ti ⁇ 2Nb, be satisfied.
  • Nb and Zr it is preferable that the relational expression Nb ⁇ 1.3Zr, or more preferably Nb ⁇ 1.5Zr, be satisfied.
  • N is a chemical element which is inevitably mixed in steel.
  • the N content is set to be 0.020% or less, or preferably 0.015% or less.
  • Co is a chemical element which improves the crevice corrosion resistance of stainless steel. Such an effect of Co is obtained in the case where the Co content is 0.01% or more. However, in the case where the Co content is more than 0.50%, such an effect of Co becomes saturated, and there is a deterioration in workability. Therefore, in the case where Co is contained, the Co content is set to be 0.01% to 0.50%. It is preferable that the lower limit of the Co content be 0.02% or more, or more preferably 0.03% or more. It is preferable that the upper limit of the Co content be 0.30% or less, or more preferably 0.10% or less.
  • Mo is effective for improving the crevice corrosion resistance of stainless steel. Such an effect is obtained in the case where the Mo content is 0.01% or more. However, in the case where the Mo content is more than 0.30%, such an effect of Mo becomes saturated, and there is a deterioration in toughness due to the formation of coarse intermetallic compounds. Therefore, in the case where Mo is added, the Mo content is set to be 0.01% to 0.30%. It is preferable that the lower limit of the Mo content be 0.02% or more, or more preferably 0.03% or more. It is preferable that the upper limit of the Mo content be 0.20% or less, or more preferably 0.10% or less.
  • W is a chemical element which improves the crevice corrosion resistance of stainless steel. Such an effect of W is obtained in the case where the W content is 0.01% or more. On the other hand, in the case where the W content is more than 0.50%, such an effect of W becomes saturated, and there is a deterioration in workability. Therefore, in the case where W is contained, the W content is set to be 0.01% to 0.50%. It is preferable that the lower limit of the W content be 0.02% or more, or more preferably 0.03% or more. It is preferable that the upper limit of the W content be 0.30% or less, or more preferably 0.10% or less.
  • V 0.01% to 0.50%
  • V is a chemical element which improves the crevice corrosion resistance of stainless steel. Such an effect of V is obtained in the case where the V content is 0.01% or more. On the other hand, in the case where the V content is more than 0.50%, such an effect of V becomes saturated, and there is a deterioration in workability. Therefore, in the case where V is added, the V content is set to be 0.01% to 0.50%, preferably 0.01% to 0.30%, or more preferably 0.01% to 0.10%.
  • B is a chemical element which improves hot workability and secondary workability, it is effective to containing B to Ti-containing steel. Such an effect of B is obtained in the case where the B content is 0.0003% or more. On the other hand, in the case where the B content is more than 0.0030%, there is a deterioration in toughness. Therefore, in the case where B is contained, the B content is set to be in the range of 0.0003% to 0.0030%. It is preferable that the lower limit of the B content be 0.0015% or more. It is preferable that the upper limit of the B content be 0.0025% or less.
  • Mg functions as a deoxidizing agent along with Al by forming Mg oxides in molten steel. Such an effect of Mg is obtained in the case where the Mg content is 0.0005% or more.
  • the Mg content is more than 0.0100%, there is a deterioration in manufacturability and a deterioration in the toughness of steel. Therefore, in the case where Mg is contained, the Mg content is limited to be in the range of 0.0005% to 0.0100%. It is preferable that the lower limit of the Mg content be 0.0010% or more. It is preferable that the upper limit of the Mg content be 0.0050% or less, or more preferably 0.0030% or less.
  • Ca is a chemical element which improves hot workability. Such an effect of Ca is obtained in the case where the Ca content is 0.0003% or more. On the other hand, in the case where the Ca content is more than 0.0030%, there is a deterioration in the toughness of steel, and there is a deterioration in corrosion resistance due to the precipitation of CaS. Therefore, in the case where Ca is added, the Ca content is limited to be in the range of 0.0003% to 0.0030%. It is preferable that the lower limit of the Ca content be 0.001% or more. It is preferable that the upper limit of the Ca content be 0.002% or less.
  • Y is a chemical element which improves cleanliness by inhibiting a decrease in the viscosity of molten steel. Such an effect of Y is obtained in the case where the Y content is 0.001% or more. On the other hand, in the case where the Y content is more than 0.20%, such an effect of Y becomes saturated, and there is a deterioration in workability. Therefore, in the case where Y is added, the Y content is limited to be in the range of 0.001% to 0.20%, or preferably 0.001% to 0.10%.
  • REM rare-earth metal: one of the chemical elements having atomic numbers of 57 through 71 such as La, Ce, or Nd
  • REM content is a chemical element which improves high-temperature oxidation resistance.
  • the REM content is 0.001% or more.
  • the REM content is more than 0.10%, such an effect of REM becomes saturated, and a surface defect occurs when hot rolling is performed. Therefore, in the case where REM is contained, the REM content is limited to be in the range of 0.001% to 0.10%. It is preferable the lower limit of the REM content be 0.005% or more. It is preferable that the upper limit of the REM content be 0.05% or less.
  • Sn is effective for improving ridging resistance by promoting the formation of a deformation zone when rolling is performed. Such an effect is obtained in the case where the Sn content is 0.001% or more. However, in the case where the Sn content is more than 0.50%, such an effect of Sn becomes saturated, and there is a deterioration in workability. Therefore, in the case where Sn is added, the Sn content is set to be 0.001% to 0.50%. It is preferable that the lower limit of the Sn content be 0.003% or more. It is preferable that the upper limit of the Sn content be 0.20% or less.
  • Sb is effective for improving ridging resistance by promoting the formation of a deformation zone when rolling is performed. Such an effect is obtained in the case where the Sb content is 0.001% or more. However, in the case where the Sb content is more than 0.50%, such an effect of Sb becomes saturated, and there is a deterioration in workability. Therefore, in the case where Sb is contained, the Sb content is set to be 0.001% to 0.50%. It is preferable that the lower limit of the Sb content be 0.003% or more. It is preferable that the upper limit of the Sb content be 0.20% or less.
  • the remainder which is other than the constituent chemical elements described above is Fe and inevitable impurities.
  • Representative examples of the inevitable impurities described here include H, O (oxygen), Zn, Ga, Ge, As, Ag, In, Hf, Ta, Re, Os, Ir, Pt, Au, and Pb.
  • H and O (oxygen) may be contained in an amount of 0.05% or less.
  • Other chemical elements may be contained in an amount of 0.3% or less.
  • Molten steel having the chemical composition described above is prepared by using a known method such as one which utilizes a converter, an electric furnace, or a vacuum melting furnace and made into a steel material (slab) by using a continuous casting method or an ingot casting-slabbing method.
  • This steel material is heated to a temperature of 1000°C to 1200°C and then subjected to hot rolling so as to have a thickness of 2.0 mm to 5.0 mm under the condition of a finishing temperature of 700°C to 1000°C.
  • the hot-rolled steel sheet which has been obtained as described above, is subjected to annealing at a temperature of 800°C to 1100°C followed by pickling, cold rolling, and cold-rolled-sheet annealing at a temperature of 700°C to 1000°C. After cold-rolled-sheet annealing has been performed, pickling is performed in order to remove scale.
  • the cold-rolled steel sheet from which scale has been removed may be subjected to skin pass rolling.
  • the present invention is effective not only for the above-mentioned cold-rolled sheet product but also for a hot-rolled sheet product.
  • Table 1-1 and Table 1-2 are combined to form Table 1
  • Table 2 Table 2-1 and Table 2-2 are combined to form Table 2
  • Table 3 Table 3-1 and Table 3-2 are combined to form Table 3
  • Table 3 had been made into steel ingots having a weight of 100 kg
  • the ingots were heated to a temperature of 1200°C and subjected to hot rolling in order to obtain hot-rolled steel sheets having a thickness of 4.0 mm.
  • the hot-rolled steel sheets were subjected to annealing at a temperature of 1100°C followed by pickling which utilized a commonly used method and subjected to cold rolling so as to have a thickness of 2.0 mm followed by annealing at a temperature of 900°C and pickling which utilized a commonly used method.
  • the quantity of surface defects was evaluated.
  • 10 steel sheets having each of the chemical compositions and by counting the number of streaks having a length in the L-direction of more than 10 mm in a region having a width of 200 mm and a length of 200 mm on the center portion of the upper surface of each of the steel sheets, a case where the average of the counted numbers was 1 or less was judged as " ⁇ " (satisfactory), and a case where the average of the counted numbers was more than 1 was judged as " ⁇ " (unsatisfactory).
  • test pieces having a length of 15 mm and a width of 20 mm were taken from the cold-rolled steel sheet, and each of the test pieces for respectively determining b and c was subjected to the corresponding annealing. Subsequently, each of the three test pieces were cut into pieces having a length of 15 mm and a width of 10 mm. Then, the Vickers hardness determined in the cross section of the cut piece was used for the evaluation. As annealing progressed, the harness of the steel sheet changed from a to c.
  • Comparative example No. 34 whose Cr content was lower than the range according to the present invention, had poor corrosion resistance.
  • Comparative example No. 35 whose Cr content was higher than the range according to the present invention, had poor toughness.
  • Comparative example No. 36 whose Ni content was lower than the range according to the present invention, had poor corrosion resistance.
  • Comparative example No. 37 whose Ti content was lower than the range according to the present invention, had poor corrosion resistance.
  • Comparative example No. 38 whose Ti content was higher than the range according to the present invention, had poor toughness and a large quantity of surface defects.
  • Comparative example No. 39 whose Nb content was lower than the range according to the present invention, had poor toughness and a large quantity of surface defects.
  • Comparative example No. 40 whose Nb content was higher than the range according to the present invention, had poor manufacturability due to a high softening temperature.
  • Comparative example No. 41 whose Zr content was lower than the range according to the present invention, had poor toughness and a large quantity of surface defects.
  • Comparative example No. 42 whose Zr content was higher than the range according to the present invention, had a large quantity of surface defects.
  • Comparative example No. 57 whose contents of Nb and Zr were both lower than the range according to the present invention, had poor toughness and a large quantity of surface defects.
  • Comparative example No. 58 whose contents of Ti and Zr were both lower than the ranges according to the present invention, and whose contents of Al and Nb were both higher than the ranges according to the present invention, had poor toughness, a large quantity of surface defects, and poor manufacturability due to a high softening temperature.
  • Fig. 1 illustrates the evaluation results of Charpy impact values and surface defects of the examples of the present invention and comparative examples (Nos. 43 through 48), whose chemical compositions were within the range according to the present invention, and in which the relational expression Nb ⁇ Zr was satisfied and the relational expression Ti ⁇ Nb was not satisfied, in a form of graph in which the horizontal axis indicates the Ti content and the vertical axis indicates the Nb content.
  • the evaluation result regarding a Charpy impact value was satisfactory
  • the evaluation regarding a surface defect was satisfactory
  • the evaluation regarding a Charpy impact value was unsatisfactory
  • the evaluation regarding a surface defect was unsatisfactory.
  • Fig. 2 illustrates the evaluation results of Charpy impact values and surface defects of the examples of the present invention and comparative examples (Nos. 49 through 54, 67, and 68), whose chemical compositions were within the range according to the present invention, and in which the relational expression Ti ⁇ Nb was satisfied and the relational expression Nb ⁇ Zr was not satisfied, in a form of graph in which the horizontal axis indicates the Nb content and the vertical axis indicates the Zr content.
  • the relational expression Nb ⁇ Zr it is necessary that the relational expression Nb ⁇ Zr be satisfied in order to realize excellent toughness and a decrease in the quantity of surface defects at the same time within the range of the chemical composition according to the present invention.
  • comparative example Nos. 55 and 56 whose chemical compositions were within the range according to the present invention, and in which the relational expression Ti ⁇ Nb or the relational expression Nb ⁇ Zr was not satisfied, were unsatisfactory in the evaluations both regarding a Charpy impact value and regarding a surface defect.
  • the ferritic stainless steel sheet according to the present invention which has excellent toughness and only a small quantity of surface defects, can preferably be used not only for parts which are required to have satisfactory corrosion resistance but also for parts which are required to have satisfactory toughness and surface quality including the inner panels of elevators, interiors, duct hoods, muffler cutters, lockers, the parts of home electrical appliances, the parts of office appliances, the interior parts of automobiles, the exhaust pipes of automobiles, building materials, the lids of drainage channel, maritime containers, house wares, kitchen appliances, the interior and exterior materials of buildings, automobile parts, escalators, railway vehicles, the chassis of electrical apparatuses and the like.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (4)

  1. Tôle d'acier inoxydable ferritique ayant une composition chimique contenant, en % massique, C: 0.001% à 0.020%, Si: 0.05% à 0.15%, Mn: 0.05% à 1.00%, P: 0.040%ou moins, S: 0.030% ou moins, Al: 0.001% à 0.15%, Cr: 20.0% à 23.0%, Ni: 0.01% à 0.80%, Cu: 0.30% à 0.80%, Ti: 0.10% à 0.50%, Nb: 0.010% à 0.150%, Zr: 0.005% à 0.150%, N: 0.020% ou moins, optionnellement un, deux, ou plus de deux choisi(s) parmi Co: 0.01% à 0.50%, Mo: 0.01% à 0.30%, et W: 0.01% à 0.50%, optionnellement un, deux, ou plus de deux choisi(s) parmi V: 0.01% à 0.50%, B: 0.0003% à 0.0030%, Mg: 0.0005% à 0.0100%, Ca: 0.0003% à 0.0030%, Y: 0.001% à 0.20%, et un métal de terre rare: 0.001% à 0.10%, optionnellement un ou les deux choisi(s) parmi Sn: 0.001% à 0.50% et Sb: 0.001% à 0.50%, et les reste étant du Fe et des impuretés inévitables, dans laquelle l'expression relationnelle (1) ci-dessous est satisfaite : Zr ≤ Nb ≤ Ti
    Figure imgb0004
     où chaque Zr, Nb, et Ti dans l'expression relationnelle (1) dénote la teneur (% massique) de l'élément chimique correspondant.
  2. La tôle d'acier inoxydable ferritique selon la revendication 1, la tôle d'acier ayant la composition chimique contenant, en % massique, un, deux, ou plus de deux choisi(s) parmi Co: 0.01% à 0.50%, Mo: 0.01% à 0.30%, et W: 0.01% à 0.50%.
  3. La tôle d'acier inoxydable ferritique selon la revendication 1 ou 2, la tôle d'acier ayant la composition chimique contenant, en % massique, un, deux, ou plus de deux choisi(s) parmi V: 0.01% à 0.50%, B: 0.0003% à 0.0030%, Mg: 0.0005% à 0.0100%, Ca: 0.0003% à 0.0030%, Y: 0.001% à 0.20%, et un métal de terre rare: 0.001% à 0.10%.
  4. La tôle d'acier inoxydable ferritique selon l'une quelconque des Revendications 1 à 3, la tôle d'acier ayant la composition chimique contenant, en % massique, un ou les deux choisi(s) parmi Sn: 0.001% à 0.50% et Sb: 0.001% à 0.50%.
EP16850651.7A 2015-09-30 2016-09-26 Tôle d'acier inoxydable ferritique Active EP3318654B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015192442 2015-09-30
PCT/JP2016/004336 WO2017056471A1 (fr) 2015-09-30 2016-09-26 Tôle d'acier inoxydable ferritique

Publications (3)

Publication Number Publication Date
EP3318654A1 EP3318654A1 (fr) 2018-05-09
EP3318654A4 EP3318654A4 (fr) 2018-05-30
EP3318654B1 true EP3318654B1 (fr) 2019-05-01

Family

ID=58423281

Family Applications (1)

Application Number Title Priority Date Filing Date
EP16850651.7A Active EP3318654B1 (fr) 2015-09-30 2016-09-26 Tôle d'acier inoxydable ferritique

Country Status (8)

Country Link
US (1) US20190055634A1 (fr)
EP (1) EP3318654B1 (fr)
JP (1) JP6142971B1 (fr)
KR (1) KR102067154B1 (fr)
CN (1) CN108138278B (fr)
ES (1) ES2727177T3 (fr)
TW (1) TWI638055B (fr)
WO (1) WO2017056471A1 (fr)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109661290A (zh) 2016-09-23 2019-04-19 塔塔钢铁荷兰科技有限责任公司 用于运动钢带的液体辅助激光纹理化的方法和装置
JP6489254B2 (ja) * 2017-04-25 2019-03-27 Ｊｆｅスチール株式会社 ステンレス冷延鋼板用素材およびその製造方法
EP3623489A4 (fr) * 2017-09-29 2020-07-08 JFE Steel Corporation Tôle d'acier inoxydable ferritique laminée à chaud et recuite et son procédé de production
BR112021000940B1 (pt) * 2018-11-09 2023-05-02 Nippon Steel Stainless Steel Corporation Chapa de aço inoxidável ferrítico
CN114207159B (zh) * 2019-07-31 2023-10-24 杰富意钢铁株式会社 奥氏体-铁素体系双相不锈钢板
CN113234994A (zh) * 2021-04-14 2021-08-10 马鞍山钢铁股份有限公司 一种屈服强度600MPa级热轧高强耐候钢板及其生产方法
CN113969378B (zh) * 2021-10-18 2022-05-20 维沃移动通信有限公司 一种合金钢材料、合金钢材料的制备方法以及电子设备

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5839732A (ja) * 1981-08-31 1983-03-08 Sumitomo Metal Ind Ltd 耐銹性および耐酸化性にすぐれたフエライト系ステンレス鋼板の製造方法
JP2623606B2 (ja) 1987-10-29 1997-06-25 住友金属工業株式会社 フェライト系ステンレス鋼の製造方法
JP4390962B2 (ja) * 2000-04-04 2009-12-24 新日鐵住金ステンレス株式会社 表面特性及び耐食性に優れた高純度フェライト系ステンレス鋼
JP4757686B2 (ja) * 2006-03-31 2011-08-24 新日鐵住金ステンレス株式会社 加工性、溶接性、耐すき間腐食性に優れた貯湯タンク用フェライト系ステンレス鋼
KR100821060B1 (ko) * 2006-12-28 2008-04-08 주식회사 포스코 내식성 및 고온 내변색성이 우수한 페라이트계스테인리스강
JP2011214060A (ja) * 2010-03-31 2011-10-27 Jfe Steel Corp フェライト系ステンレス鋼板およびその製造方法
JP2011246814A (ja) * 2010-04-30 2011-12-08 Jfe Steel Corp フェライト系ステンレス鋼板およびその製造方法
CN104685089B (zh) * 2012-12-07 2016-08-17 杰富意钢铁株式会社 铁素体系不锈钢板
CN105074035B (zh) * 2013-03-27 2018-02-16 新日铁住金不锈钢株式会社 研磨后的表面耐蚀性优异的铁素体系不锈钢及其制造方法
CN103510013B (zh) * 2013-09-29 2018-06-05 宝钢不锈钢有限公司 一种良好抗皱性的含锡铁素体不锈钢及其制造方法
JP6302690B2 (ja) * 2014-02-04 2018-03-28 新日鐵住金ステンレス株式会社 研磨後の耐食性に優れたフェライト系ステンレス鋼
JP5846339B1 (ja) * 2014-03-20 2016-01-20 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
KR20180043827A (ko) 2018-04-30
EP3318654A1 (fr) 2018-05-09
TW201718909A (zh) 2017-06-01
CN108138278B (zh) 2020-01-24
CN108138278A (zh) 2018-06-08
TWI638055B (zh) 2018-10-11
KR102067154B1 (ko) 2020-01-16
JP6142971B1 (ja) 2017-06-07
WO2017056471A1 (fr) 2017-04-06
US20190055634A1 (en) 2019-02-21
JPWO2017056471A1 (ja) 2017-10-05
ES2727177T3 (es) 2019-10-14
EP3318654A4 (fr) 2018-05-30

Similar Documents

Publication Publication Date Title
EP3318654B1 (fr) Tôle d'acier inoxydable ferritique
KR101536291B1 (ko) 표면 광택과 녹 방지성이 우수한 페라이트계 스테인리스 강판 및 그 제조 방법
EP3438310B1 (fr) Tôle d'acier inoxydable ferritique utilisée pour le soudage tig
JP4963043B2 (ja) 耐発銹性と加工性に優れた光輝焼鈍仕上げフェライト系ステンレス鋼板およびその製造方法
EP2738283A1 (fr) Couche de revêtement de zinc par immersion à chaud allié, feuille d'acier la présentant, et son procédé de fabrication
EP2687617A1 (fr) Tôle d'acier inoxydable ferritique de grande pureté présentant une excellente résistance à la corrosion et des propriétés antireflet
EP3305938A1 (fr) Élément hpf présentant une excellente résistance au délaminage et son procédé de préparation
TWI546389B (zh) Fat iron stainless steel plate
JPWO2014050011A1 (ja) フェライト系ステンレス鋼
EP3093362B1 (fr) Acier inoxydable de type ferritique et son procédé de fabrication
JP5904310B1 (ja) フェライト系ステンレス鋼およびその製造方法
JP6411881B2 (ja) フェライト系ステンレス鋼およびその製造方法
KR101940427B1 (ko) 페라이트계 스테인리스 강판
JP6146401B2 (ja) フェライト系ステンレス鋼板
JPH07126812A (ja) 耐２次加工脆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
JP2020143309A (ja) フェライト系ステンレス鋼板
JP2948416B2 (ja) 深絞り性に優れた高強度冷延鋼板及び溶融亜鉛めっき鋼板
JP3923485B2 (ja) 深絞り性に優れたフェライト単相系ステンレス鋼の製造方法
WO2023026468A1 (fr) Plaque d'acier, et article moulé et pressé
JP2023061620A (ja) マルテンサイト系ステンレス鋼板
JP3276472B2 (ja) 加工性および耐候性に優れたＦｅ−Ｃｒ合金
JP2001254154A (ja) 打ち抜き性と成形性に優れるフェライト系ステンレス冷延鋼板
TW202006154A (zh) 鋼板

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20180131

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

A4 Supplementary search report drawn up and despatched

Effective date: 20180503

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/44 20060101ALI20180425BHEP

Ipc: C22C 38/06 20060101ALI20180425BHEP

Ipc: C22C 38/00 20060101ALI20180425BHEP

Ipc: C22C 38/50 20060101ALI20180425BHEP

Ipc: C22C 38/52 20060101ALI20180425BHEP

Ipc: C22C 38/48 20060101ALI20180425BHEP

Ipc: C22C 38/46 20060101ALI20180425BHEP

Ipc: C22C 38/60 20060101ALI20180425BHEP

Ipc: C21D 9/46 20060101ALI20180425BHEP

Ipc: C21D 8/02 20060101ALI20180425BHEP

Ipc: C22C 38/02 20060101ALI20180425BHEP

Ipc: C22C 38/54 20060101ALI20180425BHEP

Ipc: C22C 38/04 20060101ALI20180425BHEP

Ipc: C22C 38/42 20060101AFI20180425BHEP

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602016013370

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C22C0038000000

Ipc: C22C0038420000

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/50 20060101ALI20181126BHEP

Ipc: C22C 38/60 20060101ALI20181126BHEP

Ipc: C21D 9/46 20060101ALI20181126BHEP

Ipc: C22C 38/02 20060101ALI20181126BHEP

Ipc: C22C 38/54 20060101ALI20181126BHEP

Ipc: C22C 38/42 20060101AFI20181126BHEP

Ipc: C22C 38/46 20060101ALI20181126BHEP

Ipc: C22C 38/44 20060101ALI20181126BHEP

Ipc: C21D 8/02 20060101ALI20181126BHEP

Ipc: C22C 38/00 20060101ALI20181126BHEP

Ipc: C22C 38/52 20060101ALI20181126BHEP

Ipc: C22C 38/48 20060101ALI20181126BHEP

Ipc: C22C 38/06 20060101ALI20181126BHEP

Ipc: C22C 38/04 20060101ALI20181126BHEP

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
INTG Intention to grant announced

Effective date: 20181214

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

Ref country code: AT

Ref legal event code: REF

Ref document number: 1126972

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190515

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602016013370

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20190501

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2727177

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20191014

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190901

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190801

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190801

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190802

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1126972

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190501

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190901

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602016013370

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602016013370

Country of ref document: DE

26N No opposition filed

Effective date: 20200204

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190930

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190930

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190926

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200401

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190926

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20190930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190930

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20200926

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20160926

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200926

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190501

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20231003

Year of fee payment: 8