EP2826878B1 - Ferritischer edelstahl - Google Patents

Ferritischer edelstahl Download PDF

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Publication number
EP2826878B1
EP2826878B1 EP13761131.5A EP13761131A EP2826878B1 EP 2826878 B1 EP2826878 B1 EP 2826878B1 EP 13761131 A EP13761131 A EP 13761131A EP 2826878 B1 EP2826878 B1 EP 2826878B1
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corrosion resistance
content
rolled
steel
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French (fr)
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EP2826878A4 (de
EP2826878A1 (de
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Takashi Samukawa
Kunio Fukuda
Masataka Yoshino
Hiroki Ota
Hiroyuki Ogata
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JFE Steel Corp
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JFE Steel Corp
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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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • C22C38/50—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a ferritic stainless steel excellent in surface quality, and excellent in corrosion resistance in a part welded with an austenitic stainless steel.
  • Patent Literature 1 discloses a ferritic stainless steel having a chemical composition consisting of, by mass%, C: 0.03% or less, Si: 1.0% or less, Mn: 0.5% or less, P: 0.04% or less, S: 0.02% or less, Al: 0.1% or less, Cr: 20.5% or more and 22.5% or less, Cu: 0.3% or more and 0.8% or less, Ni: 1.0% or less, Ti: 4(C%+N%) or more and 0.35% or less, Nb: 0.01% or less, N: 0.03% or less, C+N: 0.05% or less and the balance being Fe and inevitable impurities.
  • Ferritic stainless steels such as JIS-SUS444 and JIS-SUS430J1L are characterized by having low stress corrosion cracking sensitivity in comparison to austenitic stainless steels and not containing a large amount of Ni which is subject to wide price fluctuations, and are widely used as materials for exhaust system parts of automobiles, water tanks and building constructions.
  • austenitic stainless steels have inferior formability, especially poor ductility, comparing to austenitic stainless steels, austenitic stainless steels are used for parts which are too difficult to be formed with ferritic stainless steels. Therefore, there are many cases where one component is formed by combining austenitic stainless steels and ferritic stainless steels. Among these cases, most parts are joined together by welding, and, among welding methods, TIG welding (Tungsten Inert Gas welding) is mainly used. And good corrosion resistance is required for welded parts as well as base steels.
  • TIG welding Tungsten Inert Gas welding
  • the ferritic stainless steel according to Patent Literature 1 has good corrosion resistance in a part welded with a stainless steel of the same kind. However, there is a problem in that the corrosion resistance in a welded part is inferior to that in a base steel in the case where the ferritic stainless steel is welded with a stainless steel of the different kind such as SUS304 by performing TIG welding.
  • C or N in a steel combines with Cr, precipitating chromium carbides such as Cr 23 C 6 or chromium nitrides such as CrN 2 at grain boundaries in the thermal history of welding. These precipitations form chromium depletion layers, where Cr content is less than the base steel, in the vicinity of the grain boundaries. This phenomenon, called sensitization, causes deterioration in corrosion resistance at the grain boundaries.
  • the formation of chromium carbides and chromium nitrides are prevented by adding an appropriate amount of Ti to steel and stabilizing C and N as titanium carbonitrides with decreasing C and N contents in steel.
  • the welded part which is formed by performing TIG welding using the same ferritic stainless steels according to Patent Literature 1 has good corrosion resistance.
  • SUS304 has C content of from 0.04% to 0.05%, which is more than that of this ferritic stainless steel sheet whose C content is about 0.01%, in order to similarly prevent sensitization by adding Ti in the case where this ferritic stainless steel sheet is welded with a high carbon stainless steel such as SUS304, it is necessary to increase Ti content to about 1.0%.
  • Ti and N in molten steel react with each other to form and precipitate TiN during solidification. Since TiN has low ductility at a high temperature, it causes defects in a hot rolling process and deteriorates surface quality. Since the defects formed as described above are too deep to be eliminated during subsequent processes such as annealing of hot-rolled steel sheet, pickling of hot-rolled steel sheet, cold rolling of hot-rolled steel sheet, annealing of cold-rolled steel sheet and pickling of cold-rolled steel sheet.
  • the defects become surface defects called stringers caused by titanium nitrides, resulting in significant deterioration in surface quality of the cold-rolled, annealed and pickled steel sheet, unless performing a treatment in which a thick layer is scraped off the surface of the hot-rolled, annealed and pickled steel sheet by a grinder or the like.
  • TIG welding is generally performed under conditions in which both front and back sides of steel sheet are shielded with an inert gas so that the formation of thin oxidized layer called temper color is prevented as much as possible. Since, in a practical process, this gas shield is not sufficient, there is a problem in that sensitization described above is facilitated due to mixing of N from air.
  • the present invention has been completed in view of the situation described above, and an object of the present invention is to provide a ferritic stainless steel excellent in surface quality, and corrosion resistance in a welded part in the case that the ferritic stainless steel is welded not only with a ferritic stainless steel but also with an austenitic stainless steel.
  • the present inventors conducted exhaustive experimentations and investigations not only on the influence of the chemical composition of steel on the corrosion resistance of base steel and welded part, but also on the surface quality (stringer flaw caused by titanium nitrides) of steel sheet in order to solve the problems described above, and, as a result, obtained the following findings.
  • a ferritic stainless steel which has excellent corrosion resistance in a welded part and excellent surface quality of a cold-rolled, annealed and pickled steel sheet without having to grind the surface of a hot-rolled, annealed and pickled steel sheet and is less expensive than austenitic stainless steels containing Ni, can be achieved.
  • the ferritic stainless steel can be ideally used as materials for kitchen instruments, architectural interiors, industrial machines and automobile parts, because the ferritic stainless steel has excellent corrosion resistance in a part welded even with an austenitic stainless steel and has excellent surface quality.
  • % used when describing a chemical composition always means mass%.
  • C content be as small as possible, because C tends to combine with Cr to form Cr carbides, and intergranular corrosion is caused by Cr carbides which are formed in a heat affected zone during welding. Therefore, the C content is confined to be 0.015% or less. On the other hand, since a long time is necessary for smelting in the case where the C content is excessively small, the C content is confined to be 0.003% or more and 0.015% or less, preferably 0.003% or more and 0.012% or less from the viewpoint of corrosion resistance in a welded part, more preferably 0.003% or more and 0.010% or less.
  • Si 0.05% or more and 0.20% or less
  • the Si content is confined to be 0.05% or more.
  • the Si content is more than 0.30%, the high-speed pickling performance in a manufacturing line of carbon steel is decreased, which results in a decrease in productivity. Therefore, the Si content is confined to be 0.05% or more and 0.30% or less, preferably 0.05% or more and 0.20% or less.
  • Mn 0.10% or more and 0.35% or less
  • Mn is effective for deoxidation, the Mn content is confined to be 0.10% or more.
  • Mn is an austenite former element, Mn promotes the formation of a martensite phase in a part welded with an austenitic stainless steel (hereinafter, called the welded part of different steels).
  • the Mn content is confined to be 0.10% or more and 0.35% or less, preferably 0.10% or more and 0.25% or less.
  • the P content is confined to be 0.06% or less, preferably 0.04% or less from the viewpoint of corrosion resistance.
  • S is a chemical element which has a negative effect on corrosion resistance.
  • S in the case where S is present together with Mn, S becomes a source of pitting as a result of forming MnS, resulting in deterioration in corrosion resistance.
  • This negative effect becomes significant in the case where S content is more than 0.02%. Therefore, the S content is confined to be 0.02% or less, preferably 0.01% or less from the viewpoint of corrosion resistance, more preferably 0.006% or less.
  • Cr is a chemical element which is essential for increasing corrosion resistance of a base stainless steel by forming a passivation film on the surface of steel. Cr content of 17.0% or more is necessary in order to achieve good corrosion resistance. However, in the case where the Cr content is more than 19.0%, deterioration in corrosion resistance in the welded part with SUS304 cannot be prevented, because a martensite phase is not formed in that part. Therefore, the Cr content is confined to be 17.0% or more and 19.0% or less, preferably 17.5% or more and 18.5% or less.
  • Ni more than 0.10% and 0.30% or less
  • Ni is a chemical element which contributes to improving crevice corrosion resistance. Moreover, since Ni is an austenite former element like Mn, Ni promotes the formation of a martensite phase in the welded part of different steels. However, there is deterioration in Stress Corrosion Cracking sensitivity in the case where Ni content is more than 0.30%. In addition, Ni is an expensive chemical element. Therefore, the Ni content is confined to be more than 0.10% and 0.30% or less, preferably 0.20% or more and 0.30% or less.
  • Ti is a chemical element which is essential for achieving good corrosion resistance in the welded part of different steels when it is welded with an austenitic stainless steel as described above.
  • excessive Ti content causes an increase in the amount of precipitated TiN, which results in a significant number of stringer flaws caused by titanium nitrides, making it impossible to achieve good surface quality for a product (cold-rolled, annealed and pickled steel sheet) without performing a treatment such as grinding the surface of a hot-rolled, annealed and pickled steel sheet. Therefore, the Ti content is confined to be 0.10% or more and 0.40% or less, preferably 0.20% or more and 0.40% or less from the viewpoint of corrosion resistance in the welded part of different steels.
  • Nb 0.005% or more and less than 0.050%
  • Nb forms carbonitrides more readily than Cr and Ti.
  • the formation of Nb carbonitrides begins at a temperature higher than the temperature at which Ti carbonitrides are formed. In a cooling process thereafter, although the reason for this is not clear, the Nb carbonitrides become nucleation sites of Ti carbonitrides.
  • the lower limit of the Nb content is confined to be 0.005% or more.
  • excessive Nb content causes an increase in recrystallization temperature of a cold-rolled steel sheet, it is necessary to anneal the steel sheet at a high temperature in order to achieve sufficient mechanical properties. This increases the thickness of an oxidized layer, which is formed during finishing annealing, in comparison to the case where Nb is not contained.
  • the Nb content is confined to be 0.005% or more and less than 0.050%, more preferably 0.010% or more and less than 0.050% from the viewpoint of corrosion resistance in the welded part of different steels.
  • Mo strengthens a passivation film and significantly improves corrosion resistance.
  • Mo is a ferrite former element, even in the case where Mo content is small, a martensite phase is not formed in the welded part of different steels when it is welded with an austenitic stainless steel. This forms the welded part of different steels consisting of a ferrite phase and causes sensitization. Therefore, the Mo content is confined to be less than 0.20%.
  • Mo causes deterioration in the toughness of a hot-rolled steel sheet, it is preferable that the Mo content be less than 0.10%.
  • the lower limit of the Mo content is confined to be 0%.
  • N 0.005% or more and 0.015% or less
  • N easily combines with Cr to form Cr nitrides. It is preferable that N content be as small as possible, because Cr nitrides cause intergranular corrosion in the case where the Cr nitrides are formed in the welded part of different steels and in a heat affected zone when welding is performed. In addition, it is preferable that the N content be as small as possible in order to decrease the amount of precipitated TiN which becomes the source of stringer flaws caused by titanium nitrides.
  • the N content is confined to be 0.005% or more and 0.015% or less, preferably 0.005% or more and 0.012% or less from the viewpoint of corrosion resistance in the welded part of different steels, more preferably 0.005% or more and 0.010% or less.
  • Cu is a chemical element which improves corrosion resistance, in particular, in the case where a steel is placed in an aqueous solution or covered with weakly acidic water drops. This is because Cu which covers the surface of the base steel after dissolving in the aqueous solution or the water drops prevents the dissolution of the base steel.
  • the Cu content is confined to be 0.30% or more and 0.50% or less, preferably 0.30% or more and 0.40% or less from the viewpoint of formability at a high temperature.
  • Mg is an impurity which is mixed in mainly from the bricks of converter furnace. Mg becomes the source of various kinds of inclusion and nucleation sites of other kinds of inclusion. In addition, since the inclusions are less likely to be dissolved, even when performing a treatment such as annealing, Mg deteriorates the surface quality of not only hot-rolled, annealed and pickled steel sheet and but also product (cold-rolled, annealed and pickled steel sheet). Therefore, the Mg content is confined to be less than 0.0005%, preferably less than 0.0003%.
  • the basic chemical composition according to the present invention is as described above and the balance consists of Fe and inevitable impurities
  • Al and Sb may be further contained from the viewpoint of preventing sensitization of the welded part of different steels caused by insufficient gas shielding of TIG welding.
  • Zr and V may be contained in order to improving corrosion resistance of the welded part of different steels.
  • acceptable inevitable impurities include Ca: 0.0020% or less but it is not necessary to limit to Ca.
  • Al 0.02% or more and 0.50% or less
  • Al is a chemical element which is important in particular in the case where a gas shield for TIG welding is not satisfactory.
  • gas shield is not sufficiently effective and N in air may be mixed into weld metal.
  • sensitization cannot be completely prevented through adding Ti only, if the content of C and N is more than the solid solubility limit of martensite phase.
  • it is effective to add Al in advance to prevent sensitization. This is because Al stabilizes N in weld metal as AlN. This effect can be realized by confining Al content to be 0.02% or more.
  • the Al content is more than 0.50%, non-metal inclusions are formed in a slab, which results in deterioration in surface quality of hot-rolled steel sheet and cold-rolled steel sheet. Therefore, in the case where Al is contained, it is preferable that the Al content be 0.02% or more and 0.50% or less. A more preferable lower limit of the Al content is 0.10%, further more preferably 0.15%. A more preferable upper limit of the Al content is 0.30%.
  • Sb is a chemical element which is better to add in the case where a component has a complicated shape, since Sb is, like Al, effective for stabilizing N mixed from air in the case where a gas shield of TIG welding is not sufficiently effective.
  • Sb content is excessively large, non-metal inclusions are formed in a slab, which results in deterioration in surface quality of hot-rolled steel sheet and cold-rolled steel sheet. Therefore, in the case where Sb is contained, it is preferable that the Sb content be 0.005% or more and 0.30% or less, more preferably 0.005% or more and 0.10% or less from the viewpoint of the surface quality of product (cold-rolled, annealed and pickled steel sheet).
  • Zr is a chemical element which is effective for improving corrosion resistance in the welded part not only of same steels but also of different steels by forming, like Ti, carbonitrides more readily than Cr.
  • Zr is more expensive than Ti and, in the case where Zr content is excessively large, Zr forms intermetallic compounds, which results in deterioration in toughness of hot-rolled steel sheet. Therefore, in the case where Zr is contained, it is preferable that the Zr content be 0.05% or more and 0.60% or less, more preferably 0.15% or more and 0.35% or less.
  • V 0.02% or more and 0.50% or less
  • V is also a chemical element which is effective for improving corrosion resistance in the welded part not only of same steels but also of different steels by forming, like Ti, carbonitrides more readily than Cr. However, this effect of V is smaller than that of Ti. Also, V is expensive. Therefore, in the case where V is contained, it is preferable that the V content be 0.02% or more and 0.50% or less, more preferably 0.02% or more and 0.05% or less.
  • Steel having a chemical composition described above is smelted using a well-known method such as a converter furnace, an electric furnace or a vacuum melting furnace, and the smelted steel is made into a steel material (slab) using a continuous casting method or an ingot casting-blooming method.
  • This steel material is heated at a temperature in the range from 1100°C to 1250°C for a duration of from 1 hour to 24 hours and, or directly without heating, hot-rolled into a hot-rolled steel sheet.
  • the hot-rolled steel sheet is generally subjected to annealing at a temperature in the range from 800°C to 1100°C for a duration of from 1 minute to 10 minutes, this annealing may be omitted depending on use application.
  • the hot-rolled steel sheet is cold-rolled into a cold-rolled steel sheet, and the cold-rolled steel sheet is made a product by performing finishing annealing.
  • cold rolling is performed with a rolling reduction ratio of 50% or more from the viewpoint of elongation performance, bending performance, press forming performance and shape leveling.
  • finishing annealing of cold-rolled steel sheet be generally performed at a temperature in the range from 800°C to 950°C in the case of No. 2B finish in accordance with JIS G 0203.
  • the product be manufactured in an inexpensive process using a high-speed pickling method (refer to Patent Literature 2) of annealing and pickling line for carbon steel as described above, and, in this case, it is preferable that annealing temperature be in the range from 800°C to 900°C.
  • annealing temperature be in the range from 800°C to 900°C.
  • finishing annealing using BA annealing method is effective. As described above, there is no problem in that a treatment such as polishing is performed after cold rolling or forming has been performed in order to achieve further better surface quality.
  • these hot-rolled sheets were subjected to annealing in air at a temperature of 950°C for a duration of 1 minute, followed by a surface treatment using shot blasting with glass beads, and descaling by pickling in which the steel sheets were dipped in a sulfuric acid solution containing sulfuric acid in a concentration of 20 mass% at a temperature of 80°C for a duration of 120 seconds and then in a mixed acid solution containing nitric acid in a concentration of 15 mass% and hydrofluoric acid in a concentration of 3 mass% at a temperature of 55°C for a duration of 60 seconds.
  • the hot-rolled steel sheets were cold-rolled into cold-rolled steel sheets having a thickness of 1.0 mm, subjected to annealing in a furnace in air at a temperature of 900°C for a duration of 1 minute and made cold-rolled and annealed steel sheets.
  • These cold-rolled and annealed steel sheets were subjected to electrolytic descaling with the steel sheet being a positive electrode for three times in a solution containing NaSO 4 in a concentration of 20 mass% at a temperature of 80°C with a current of 3 A/dm 2 for a duration of 10 seconds, and descaling in a mixed acid solution containing nitric acid in a concentration of 5 mass% and hydrofluoric acid in a concentration of 3 mass% at a temperature of 55°C for a duration of 30 seconds in order to have cold-rolled, annealed and pickled steel sheets.
  • the surface quality of the obtained cold-rolled, annealed and pickled steel sheets was evaluated by a visual inspection.
  • a neutral salt spray cyclic corrosion test was carried out in accordance with JIS H 8502 (1999 ).
  • the obtained results are given in Table 2.
  • the evaluation standards of the tests will be described hereafter.
  • Examples No. 1 through No. 6 and No. 33 having a chemical composition in the range according to the present invention were excellent in corrosion resistance and surface quality in all evaluation items.
  • comparative example No. 9 having low Cr content of 16.2% was poor in corrosion resistance, as indicated by its large rust areas.
  • Comparative example No. 10 having high Cr content of 19.4% was poor in corrosion resistance, as indicated by its large rust area in the welded part of different steels. This is thought to be because a martensite phase is not formed in the welded part of different steels due to the large content of Cr which is a ferrite former element.
  • Comparative example No. 11 having low Ti content of 0.07% was poor in corrosion resistance, as indicated by its large rust area in the welded part of different steels.
  • These hot-rolled and annealed steel sheet coils were shot blasted with iron beads, descaled by pickling in which the steel sheet coils were dipped in a sulfuric acid solution containing sulfuric acid in a concentration of 20 mass% at a temperature of 80°C for a duration of 120 seconds and then in a mixed acid solution containing nitric acid in a concentration of 15 mass% and hydrofluoric acid in a concentration of 3 mass% at a temperature of 55°C for a duration of 60 seconds.
  • these hot-rolled and annealed steel sheets coils were cold-rolled into cold-rolled steel sheet coils having a thickness of 1.0 mm, subjected to annealing in a furnace in an atmosphere of a coke oven gas having an air ratio of 1.3 at a temperature of 900°C for a duration of 2 minutes, electrolytic descaling with the steel sheet being a positive electrode for three times in a solution containing NaSO 4 in a concentration of 20 mass% at a temperature of 80°C with a current of 3 A/dm 2 for a duration of 10 seconds, and descaling in a mixed acid solution containing nitric acid in a concentration of 5 mass% and hydrofluoric acid in a concentration of 3 mass% at a temperature of 55°C for a duration of 30 seconds in order to obtain cold-rolled, annealed and pickled steel sheets.
  • Examples No. 13 through 16 and No. 18 having a chemical composition in the range according to the present invention were excellent in corrosion resistance and surface quality in all evaluation items.
  • Comparative example No. 17 had a poorer surface quality than the inventive examples.
  • comparative example No. 21 had Si content of 0.33% and Nb content of 0.003% out of the range according to the present invention
  • comparative example No. 22 had Si content of 0.45% and Mg content of 0.0010% more than the range according to the present invention, some residual scale was found, and both were poor in corrosion resistance after cold rolling, annealing and pickling.
  • these hot-rolled sheets were subjected to annealing in air at a temperature of 950°C for a duration of 1 minute, followed by a surface treatment using shot blasting with glass beads, and descaling by pickling in which the steel sheets were dipped in a sulfuric acid solution containing sulfuric acid in a concentration of 20 mass% at a temperature of 80°C for a duration of 120 seconds and then in a mixed acid solution containing nitric acid in a concentration of 15 mass% and hydrofluoric acid in a concentration of 3 mass% at a temperature of 55°C for a duration of 60 seconds.
  • the hot-rolled steel sheets were cold-rolled into cold-rolled steel sheets having a thickness of 1.0 mm, subjected to annealing in a reducing atmosphere (H 2 : 5 volume%, N 2 : 95 volume%, dewpoint: -40°C) at a temperature of 900°C for a duration of 1 minute and made cold-rolled and annealed steel sheets.
  • a reducing atmosphere H 2 : 5 volume%, N 2 : 95 volume%, dewpoint: -40°C
  • the surface quality of the obtained cold-rolled, annealed and pickled steel sheets was evaluated by a visual inspection.
  • Example 1 Two kinds of samples for evaluating the corrosion resistance of the base steel sheet were prepared as was done in Example 1.
  • a neutral salt spray cyclic corrosion test was carried out in accordance with JIS H 8502 (1999 ).
  • the obtained results are given in Table 6.
  • the evaluation standards were similar to those in Example 1.
  • Examples No. 23 through 26 and No. 28 were excellent in corrosion resistance and surface quality in all evaluation items.
  • Examples No. 25 through No. 26 and No. 28 to which Al, Sb Zr and V were added were significantly excellent in corrosion resistance even in the welded part of different steels using a SUS304.
  • comparative example No. 29 had Cr content of 16.7% less than the range according to the present invention, it was poor in corrosion resistance, as indicated by its large rust area.
  • comparative example No. 30 had Cr content of 19.7% more than the range according to the present invention, it was poor in corrosion resistance, as indicated by its large rust area in the welded part with different steels. This is because a martensite phase is not formed in the welded part of different steels due to the large content of Cr, which is a ferrite former element.
  • comparative example No. 31 had Si content of 0.36% and Mo content of 0.40% more than the range according to the present invention, some residual scale was found on the surface of the base steel sheet. And it was poor not only in corrosion resistance after cold rolling, annealing and pickling, but also in corrosion resistance in the welded part of different steels using a SUS304 in which, in particular, gas shield was not sufficient.
  • comparative example No. 32 had Si content of 0.50% and Nb content of 0.10% more than the range according to the present invention, some residual scale was found on the surface of the base steel sheet, and it was poor in corrosion resistance after cold rolling, annealing and pickling.
  • a ferritic stainless steel excellent in corrosion resistance of base steel sheet, corrosion resistance in the welded part of same steels, corrosion resistance in the welded part of different steels using a SUS304 and the surface quality of cold-rolled, annealed and pickled sheet can be obtained without grinding the surface of hot-rolled, annealed and pickled steel sheet.
  • the ferritic stainless steel according to the present invention can be preferably used as a material for parts which need corrosion resistance such as kitchen and house wares, architectural interior and exterior, building parts, the interior of an elevator and an escalator, electric appliances and automobile parts.

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

Claims (2)

  1. Ferritischer Edelstahl, der eine chemische Zusammensetzung hat, die in Massen-% besteht aus: C: 0,003% oder mehr und 0,015% oder weniger, Si: 0,05% oder mehr und 0,20% oder weniger, Mn: 0,10% oder mehr und 0,35% oder weniger, P: 0,06% oder weniger, S: 0,02% oder weniger, Cr: 17,0% oder mehr und 19,0% oder weniger, Ni: mehr als 0,10% und 0,30% oder weniger, Ti: 0,10% oder mehr und 0,40% oder weniger, Nb: 0,005% oder mehr und weniger als 0,050%, Mo: weniger als 0,20%, N: 0,005% oder mehr und 0,015% oder weniger, Cu: 0,30% oder mehr und 0,50% oder weniger, Mg: weniger als 0,0005% und wahlweise weiterhin umfassend in Massen-%, Al: 0,02% oder mehr und 0,50% oder weniger, Sb: 0,005% oder mehr und 0,300% oder weniger, Zr: 0,05% oder mehr und 0,60% oder weniger und/oder V: 0,02% oder mehr und 0,50% oder weniger, wobei die Restmenge Fe und unvermeidbare Verunreinigungen sind.
  2. Ferritischer Edelstahl nach Anspruch 1, wobei der Stahl eine chemische Zusammensetzung hat, die Al: 0,10% oder mehr und 0,50% oder weniger in Massen-% umfasst.
EP13761131.5A 2012-03-13 2013-03-07 Ferritischer edelstahl Active EP2826878B1 (de)

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JP5534119B1 (ja) * 2012-09-25 2014-06-25 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼
CN105408511B (zh) * 2013-07-29 2018-09-07 杰富意钢铁株式会社 焊接部的耐腐蚀性优良的铁素体系不锈钢
KR101850231B1 (ko) * 2014-01-08 2018-04-18 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스강 및 그 제조 방법
KR20180114240A (ko) * 2014-01-08 2018-10-17 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스강 및 그 제조 방법
JP6137089B2 (ja) * 2014-09-02 2017-05-31 Ｊｆｅスチール株式会社 冷延鋼板の製造方法および冷延鋼板の製造設備
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TW201348463A (zh) 2013-12-01
CN104169451A (zh) 2014-11-26
EP2826878A4 (de) 2015-02-25
CN104169451B (zh) 2017-11-28
EP2826878A1 (de) 2015-01-21
TWI510645B (zh) 2015-12-01
JP5376099B1 (ja) 2013-12-25
WO2013136736A1 (ja) 2013-09-19
US20150023832A1 (en) 2015-01-22
KR20140127862A (ko) 2014-11-04
JPWO2013136736A1 (ja) 2015-08-03

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