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
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
  • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
  • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
  • B23K35/001—Interlayers, transition pieces for metallurgical bonding of workpieces
  • B23K35/004—Interlayers, transition pieces for metallurgical bonding of workpieces at least one of the workpieces being of a metal of the iron group
• • 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
  • 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
  • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
• • 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 ferritic stainless steel with corrosion resistance, in particular, excellent corrosion resistance in a weld zone which is formed when the ferritic stainless steel is welded together with austenitic stainless steel, and with excellent surface quality.
• Patent Literature 1 discloses a ferritic stainless steel having a chemical composition containing, 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 of JIS- SUS444, JIS-SUS430J1L, and the like have characteristics such as having lower stress corrosion cracking sensitivity than austenitic stainless steels and not containing Ni whose price varies largely, these stainless steels are widely used as materials for exhaust system parts of automobiles and water tanks and building materials.
• austenitic stainless steels are used as materials for parts which are too difficult to form from ferritic stainless steels. Therefore, there are many cases where one component is formed by connecting parts made of austenitic stainless steels and that of ferritic stainless steels. In these cases, parts are joined together by performing welding in most cases, and, among welding methods, TIG welding (Tungsten Inert Gas welding) is mainly used, and good corrosion resistance is required for the weld zone as well as the base metal.
• TIG welding Tungsten Inert Gas welding
• the ferritic stainless steel according to Patent Literature 1 has good corrosion resistance in a weld zone in the case where steels of the same grade are welded. However, there is a problem in that the corrosion resistance in a weld zone is less than that of base metals in the case where the ferritic stainless steel is welded together with another kind of steel such as SUS304 by performing TIG welding.
• a method is used in which the formation of Cr-carbides and Cr-nitrides are prevented by reducing C and N in steel, adding an appropriate amount of Ti, and fixing C and N as a titanium carbonitride.
• the weld zone which is formed by performing TIG welding on sheets of the same ferritic stainless steel according to Patent Literature 1, has good corrosion resistance.
• the defects formed as described above are too deep to be eliminated during annealing of a hot-rolled sheet and acid pickling and further during cold rolling, annealing of a cold-rolled sheet and acid pickling, the defects become surface defects called stringers caused by titanium nitrides, unless performing a treatment such as surface grinding in which a thick layer is shaved off the surface of the hot-rolled, annealed and pickled steel sheet, which results in a significant decrease in the surface quality of the cold-rolled, annealed and pickled steel sheet.
• the present invention has been completed in view of the situation described above, and the present invention aims to provide a ferritic stainless steel with excellent corrosion resistance in a weld zone which is obtained even when the ferritic stainless steel is welded together with an austenitic stainless steel and to provide a ferritic stainless steel with excellent surface quality.
• the present inventors in order to solve the problems described above, conducted close examinations and investigations regarding the influence of the chemical composition of steel on the corrosion resistance of a base metal and a weld zone and on the occurrence behavior of surface defects (a scab, a pin hole, a linear scab, a shape defect such as stringers caused by titanium nitrides, and a color defect of a white stripe type) of a steel sheet, and, as a result, obtained the following knowledge.
• surface defects a scab, a pin hole, a linear scab, a shape defect such as stringers caused by titanium nitrides, and a color defect of a white stripe type
• Sensitization can be prevented to some extent by making the microstructure of a weld zone, which is formed by welding a ferritic stainless steel and an austenitic stainless steel, a martensite phase, in which the solid solubility limits of C and N are large, by adjusting the contents of chemical elements promoting the formation of a ferritic phase, which are so-called ferritic former elements.
• sensitization can be prevented due to the formation of AlN in the weld zone by adding Al. Sensitization can also be prevented due to the formation of the compounds of Sb and N in a weld zone by adding Sb.
• a stringer flaw caused by titanium nitrides is mainly caused by TiN which grows at the columnar grain boundaries, because TiN which is present in the part of columnar grains grows to a large size.
• a stringer flaw caused by titanium nitrides is hardly caused by TiN in other parts than that in the part of columnar grains, because it is highly probable that this kind of TiN is removed in normal post-processes such as acid pickling of a hot-rolled sheet and acid pickling of a cold-rolled sheet.
• Ferritic stainless steel with excellent corrosion resistance in a weld zone and surface quality having a chemical composition containing, by mass %, C: 0.003% or more and 0.012% or less, Si: 0.30% or more and 0.60% or less, Mn: 0.10% or more and 0.35% or less, P: 0.040% or less, S: 0.020% or less, Cr: 17.0% or more and 19.0% or less, Ni: more than 0.10% and 0.30% or less, Ti: 0.10% or more and 0.40% or less, Nb: 0.005% or more and less than 0.050%, Mo: 0.20% or less, N: 0.005% or more and 0.015% or less, Cu: 0.3% or more and 0.5% or less, Mg: less than 0.0005%, and the balance being Fe and inevitable impurities.
• the ferritic stainless steel with excellent corrosion resistance in a weld zone and surface quality according to any one of items [1] to [3], the steel having the chemical composition further containing, by mass %, one or two of Zr: 0.01% or more and 0.60% or less and V: 0.01% or more and 0.50% or less.
• the ferritic stainless steel according to the present invention can be suitably used as materials for kitchen instruments, architectural interiors, industrial machineries, and automobile parts, because the ferritic stainless steel has excellent corrosion resistance in a weld zone and surface quality when the ferritic stainless steel is welded even together with an austenitic stainless steel.
• % 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 because intergranular corrosion is caused by Cr carbides which are formed in a heat affected zone when welding is performed. Therefore, the C content is set to be 0.012% 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 set to be 0.003% or more and 0.012% or less, preferably 0.003% or more and 0.010% or less.
• Si 0.30% or more and 0.60% or less
• Si is a chemical element which is important in the present invention.
• Si is added in an appropriate mount, there is a decrease in the solubility product of Ti and N and therefore the precipitation of Ti carbonitrides is promoted at a temperature higher than that at which columnar grains are formed.
• the amount of N in steel it is difficult for TiN to precipitate at the columnar grain boundaries when columnar grains grow afterwards.
• the chemical composition according to the present invention by adding Si in an amount of 0.30% or more, it is possible to suppress the precipitate of TiN at the columnar grain boundaries, which causes a stringer flaw caused by titanium nitrides.
• the Si content is set to be 0.30% or more and 0.60% or less, preferably 0.40% or more and 0.50% or less.
• Mn 0.10% or more and 0.35% or less Since Mn is effective for deoxidation, the Mn content is set to be 0.10% or more. In addition, since Mn is a chemical element promoting the formation of an austenite phase (an austenite former element), Mn promotes the formation of a martensite phase in a weld zone which is formed when a ferritic stainless steel is welded together with an austenitic stainless steel (hereinafter, called the weld zone of steels of different grades). However, in the case where the Mn content is excessively large, Mn combines with S in the steel to form MnS which is a soluble sulfide, which results in a decrease in corrosion resistance. Therefore, the Mn content is set to be 0.10% or more and 0.35% or less, preferably 0.10% or more and 0.25% or less.
• the P is a chemical element which has a negative effect on corrosion resistance, and, moreover, which decreases hot formability. In particular, these tendencies become significant in the case where the P content is more than 0.040%. Therefore, the P content is set to be 0.040% or less, preferably 0.030% or less.
• 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, which results in a decrease in corrosion resistance.
• This negative effect becomes significant in the case where S content is more than 0.020%. Therefore, the S content is set to be 0.020% or less, preferably 0.010% or less, more preferably 0.006% or less.
• Cr is a chemical element which is essential for increasing the corrosion resistance of a base metal by forming a passivation film on the surface of a stainless steel.
• Cr content 17.0% or more is necessary in order to achieve good corrosion resistance, in the case where the Cr content is more than 19.0%, a decrease in corrosion resistance cannot be prevented in the weld zone of steels of different grades with SUS304, because a martensite phase cannot be formed in the weld zone. Therefore, the Cr content is set 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
• Nb 0.005% or more and less than 0.050%
• the Nb content is set to be 0.005% or more and less than 0.050%, preferably 0.01% or more and less than 0.050%.
• the Ti content is set to be 0.10% or more and 0.40% or less, preferably 0.20% or more and 0.40% or less.
• Mo is a chemical element which strengthens a passivation film and significantly increases corrosion resistance, and these effects are realized in the case where the Mo content is 0.01% or more.
• Mo is a chemical element promoting the formation of a ferrite phase, which is a so-called ferrite former element, a martensite phase is not formed in the weld zone of steels of different grades which is formed when a ferritic stainless steel is welded together with an austenitic stainless steel, in the case where the Mo content is more than 0.20%, and a ferrite phase containing a small amount of C and N in the form of solid solution is formed, which results in sensitization not being prevented. Therefore, the Mo content is set to be 0.20% or less. In addition, since Mo causes a decrease in the toughness of a hot-rolled steel sheet, it is preferable that the Mo content be 0.10% or less.
• N 0.005% or more and 0.015% or less
• N tends to combine with Cr to form Cr nitrides. It is preferable that the N content be as small as possible, because Cr nitrides cause intergranular corrosion in the case where Cr nitrides are formed in the weld zone of steels of different grades and in a heat affected zone when welding is performed. In addition, it is preferable that N content be as small as possible, because N is a chemical element which causes stringer flaws caused by titanium nitrides. However, since smelting takes a long time in the case where the N content is excessively small, the N content is set to be 0.005% or more and 0.015% or less, preferably 0.005% or more and 0.012% or less.
• Cu is a chemical element which increases corrosion resistance, in particular in the case where a steel sheet is placed in an aqueous solution or covered with weakly acidic water drops. This is presumed to be because Cu suppresses the dissolution of the base metal of the steel sheet by first dissolving at a certain electrochemical potential in the aqueous solution or the water drops and then by covering the surface of the base metal.
• the Cu content is set to be 0.3% or more and 0.5% or less, preferably 0.3% or more and 0.4% or less.
• Mg is an impurity which is mixed in mainly from the bricks of a converter furnace. Since Mg becomes the source of various kinds of inclusion and nucleation sites of other kinds of inclusion even if the amount of Mg which is mixed in is small, and since Mg is less likely to reform into a solid solution even when a treatment such as annealing is performed, Mg decreases the surface quality of a hot-rolled, annealed and pickled steel sheet and a cold-rolled, annealed and pickled steel sheet. Therefore, the Mg content is set to be less than 0.0005%, preferably less than 0.0003%.
• the basic chemical composition according to embodiments of the present invention is as described above and the balance consists of Fe and inevitable impurities.
• Al and Sb may be further added as selective chemical elements from the viewpoint of forming a gas shield for TIG welding and preventing the sensitization of the weld zone of steels of different grades.
• Zr and V may be added as selective chemical elements in order to improve the corrosion resistance of the weld zone of steels of different grades.
• inevitable impurities Ca: 0.0020% or less is acceptable.
• Al 0.01% or more and 0.5% or less
• Al fixes N which is mixed in the weld metal and forms AlN as a result of combining with N.
• This effect can be realized in the case where the Al content is 0.01% or more.
• the Al content is excessively large, non-metal inclusions are formed at the slab stage, which results in a decrease in surface quality, and which results in a decrease in the toughness of a hot-rolled sheet. Therefore, in the case where Al is added, it is preferable that the Al content be 0.01% or more and 0.5% or less, preferably 0.1% or more and 0.5% or less, more preferably 0.15% or more and 0.25% or less.
• Sb is a chemical element that is, like Al, effective for fixing N which is mixed in from air in the case where a gas shield for TIG welding is not sufficiently effective.
• Sb content is excessively large, non-metal inclusions are formed at the slab stage, which results in a decrease in the surface quality, and which results in a decrease in the toughness of a hot-rolled sheet. Therefore, in the case where Sb is added, it is preferable that the Sb content be 0.05% or more and 0.30% or less, more preferably 0.05% or more and 0.15% or less.
• Zr is a chemical element which is preferably added in consideration of the corrosion resistance of a weld zone, because Zr increases corrosion resistance in the weld zone of steels of the same grade and in the weld zone of steels of different grades by forming, like Ti, carbonitrides more preferentially than Cr.
• Zr is more expensive than Ti and forms intermetallic compounds in the case where Zr content is excessively large, which results in a decrease in the toughness of a hot-rolled sheet. Therefore, in the case where Zr is added, it is preferable that the Zr content be 0.01% or more and 0.60% or less, more preferably 0.1% or more and 0.35% or less.
• V 0.01% or more and 0.50% or less
• V is also a chemical element which is effective for increasing corrosion resistance in the weld zone of steels of the same grade and in the weld zone of steels of different grades by forming, like Ti, carbonitrides more preferentially than Cr.
• This effect can be realized in the case where the V content is 0.01% or more.
• the V content is more than 0.50%, there is a decrease in mechanical properties. Therefore, in the case where V is contained, it is preferable that the V content be 0.01% or more and 0.50% or less, more preferably 0.02% or more and 0.05% or less.
• Steel having the chemical composition described above is smelted using a well-known method such as one using a converter furnace, an electric furnace, or a vacuum melting furnace, and the steel is made into a steel material (slab) using a continuous casting method or an ingot casting and slabbing process.
• This steel material is heated at a temperature of 1100° C. to 1250° C. for a duration of 1 to 24 hours and hot-rolled into a hot-rolled sheet, or hot-rolled into a hot-rolled sheet without undergoing such heating.
• the hot-rolled steel sheet is normally subjected to annealing of a hot-rolled sheet at a temperature of 800° C. to 1100° C. for a duration of 1 to 10 minutes. However, annealing of a hot-rolled sheet may be omitted depending on use application. Then, after being subjected to pickling of a hot-rolled sheet, the hot-rolled sheet is cold-rolled into a cold-rolled sheet, and the cold-rolled sheet is made into a product sheet by performing finishing annealing. It is preferable that cold rolling be performed with a rolling reduction ratio in thickness of cold rolling of 50% or more in order to achieve good ductility, bending performance, and press forming performance and in order to perform shape leveling. It is preferable that recrystallization annealing of a cold-rolled steel sheet be performed at a temperature of 800° C. to 950° C. in the case of No. 2B finish in order to achieve good mechanical properties and pickling performance.
• the product be manufactured in an inexpensive process using a rapid pickling method which uses an annealing and pickling line for carbon steel which utilizes a line for manufacturing carbon steel as described above, and, in this case, it is most preferable that the annealing temperature be 800° C. to 900° C.
• Ferritic stainless steels having chemical compositions of examples No. 1 through No. 8 and comparative examples No. 9 through No. 12 given in Table 1 were smelted using a small vacuum melting furnace having a capacity of 50 kg. These ingots were heated at a temperature of 1150° C. in a furnace under an Ar gas purge and hot-rolled into hot-rolled sheets having a thickness of 3.5 mm.
• these hot-rolled sheets were subjected to annealing of a hot-rolled sheet in air at a temperature of 950° C. for a duration of 1 minute, and a surface treatment using shot blasting with glass beads. Then, descaling was performed using a pickling process in which the steel sheets were dipped in a sulfuric acid solution containing sulfuric acid at 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 at a concentration of 15 mass % and hydrofluoric acid at a concentration of 3 mass % at a temperature of 55° C. for a duration of 60 seconds.
• the hot-rolled 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 in order to obtain cold-rolled and annealed sheets.
• These cold-rolled and annealed sheets were subjected to electrolytic descaling three times in a solution containing Na 2 SO 4 at a concentration of 20 mass % at a temperature of 80° C.
• Electrode tungsten electrode of 1.6 mm
• Shield gas face bead side Ar 20 Liter/min, back bead side Ar 20 Liter/min
• the steels having chemical compositions No. 1 through No. 8 which were within the range according to preferred embodiments of the present invention were excellent in terms of corrosion resistance and surface quality in the cold-rolled, annealed and pickled sheet state, in the polished sheet state, in the weld zone of steels of the same grade and in the weld zone of the steels of different grades with SUS304.
• comparative example No. 10 which had a large Cr content of 19.5% had a large rust area in the weld zone of steels of different grades, which means that No. 10 was poor in terms of corrosion resistance. It is thought to be because a martensite phase was not formed in the weld zone of steels of different grades due to the high content of Cr which is a ferrite former element.
• comparative example No. 11 which had a small Ti content of 0.08% had large rust areas in the weld zone of steels of the same grade and in the weld zone of steels of different grades, which means that No. 11 was poor in terms of corrosion resistance.
• steels having chemical compositions of examples No. 13 through No. 18 and comparative examples No. 19 through No. 22 given in Table 3 were smelted using a VOD (Vacuum Oxygen Decarburization) having a capacity of 150 ton and cast into slabs by performing continuous casting. These slabs were heated at a temperature of 1150° C. and hot-rolled into hot-rolled steel sheets in a coiled state having a thickness of 3.5 mm. Then, these hot-rolled sheets were subjected to annealing in an atmosphere of a coke oven gas having an air ratio of 1.3 at a temperature of 950° C.
• VOD Vauum Oxygen Decarburization
• the hot-rolled sheets were cold-rolled into cold-rolled sheets 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 three times in a solution containing Na 2 SO 4 at a concentration of 20 mass % at a temperature of 80° C. with a current of 3 Ampere /dm 2 for a duration of 10 seconds and descaling in a mixed acid solution containing nitric acid at a concentration of 5 mass % and hydrofluoric acid at 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.
• corrosion resistance was evaluated by performing a CCT.
• these cold-rolled, annealed and pickled sheets were polished to #600 finish and used for corrosion resistance evaluation, a corrosion resistance test on a weld zone and a corrosion resistance test on the weld zone of steels of different grades with SUS304.
• the steels having chemical compositions No. 13 to No. 18 which were within the range according to preferred embodiments of the present invention were excellent in terms of corrosion resistance and surface quality in the cold- rolled, annealed and pickled sheet state, in the polished sheet state, in the weld zone of steels of the same grade and in the weld zone of the steels of different grades with SUS304.
• comparative example No. 19 which had a Mo content of 0.35% which was larger than the range according to preferred embodiments of the present invention had a large rust area in the weld zone of steels of different grades, which means that No. 19 was poor in terms of corrosion resistance.
• comparative example No. 20 which had a large Cr content of 19.7% had a large rust area in the weld zone of steels of different grades, which means that No. 20 was poor in terms of corrosion resistance. It is thought to be because a martensite phase was not formed in the weld zone of steels of different grades due to the high content of Cr which is a ferrite former element.
• comparative example No. 21 which had Si content which was less than the range according to preferred embodiments of the present invention and comparative example No. 22 which had small Si content and large Mg content were poor in terms of surface quality.
• these hot-rolled sheets were subjected to annealing of a hot-rolled sheet in air at a temperature of 950° C. for a duration of 1 minute, 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 at 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 at a concentration of 15 mass % and hydrofluoric acid at a concentration of 3 mass % at a temperature of 55° C. for a duration of 60 seconds.
• the hot-rolled 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 in order to obtain cold-rolled and annealed sheets.
• a reducing atmosphere H 2 : 5 volume %, N 2 : 95 volume %, dewpoint: ⁇ 40° C.
• These cold-rolled and annealed sheets were subjected to descaling using electrolysis (10 Ampere /dm 2 for 2 seconds) two times in a solution containing nitric acid at a concentration of 15 mass % and hydrochloric acid in an concentration of 0.5 mass % at a temperature of 50° C. in order to obtain cold-rolled, annealed and pickled sheets.
• Electrode tungsten electrode of 1.6 mm
• Shield gas face bead side Ar +20 vol % N 2 20 Liter/min, back bead side Ar+20 vol % N 2 20 Liter/min
• the steels having chemical compositions No. 23 to No. 28 and No. 33 which were within the range according to preferred embodiments of the present invention were excellent in terms of corrosion resistance and surface quality in the cold-rolled, annealed and pickled sheet state, in the polished sheet state, in the weld zone of steels of the same grade even in the case of an insufficient gas shield and in the weld zone of the steels of different grades with SUS304 even in the case of an insufficient gas shield.
• No. 25 through No. 28 and No. 33, to which Al, Sb, Zr and V were added were excellent in terms of corrosion resistance in the weld zone of steels of different grades with SUS304 even in the case of an insufficient gas shield.
• comparative example No. 30 which had a large Cr content of 19.8% had a large rust area in the weld zone of steels of different grades, which means that No. 30 was poor in terms of corrosion resistance. It is thought to be because a martensite phase was not formed in the weld zone of steels of different grades due to the high content of Cr which is a ferrite former element.
• comparative example No. 31 which had a small Si content of 0.15% and a large Mo content of 0.4% was poor in terms of surface quality and, in particular, in terms of corrosion resistance and surface quality in the weld zone of steels of the same grade in the case of an insufficient gas shield and in the weld zone of steels of different grades with SUS304 in the case of an insufficient gas shield.
• a ferritic stainless steel with excellent corrosion resistance of base metal, corrosion resistance in the weld zone of steels of the same grade, corrosion resistance in the weld zone of steels of different grades with SUS304 and with excellent surface quality of a cold-rolled, annealed and pickled sheet can be obtained without grinding the surface of a hot-rolled, annealed and pickled steel sheet.
• the present invention can be suitably used as a material for parts, of which corrosion resistance is required, such as house wares, kitchen instrument, architectural interior and exterior, metal fittings in architecture, the interior of an elevator and an escalator, electric appliances, and automobile components.

Landscapes

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

Applications Claiming Priority (3)

Publications (1)

Family

ID=48535012

Family Applications (1)

Country Status (9)

Cited By (4)

Families Citing this family (9)

Citations (3)

Family Cites Families (8)

• 2012
  • 2012-11-27 WO PCT/JP2012/007593 patent/WO2013080518A1/ja active Application Filing
  • 2012-11-27 EP EP12852604.3A patent/EP2787096B1/en active Active
  • 2012-11-27 ES ES12852604.3T patent/ES2602800T3/es active Active
  • 2012-11-27 US US14/359,782 patent/US20140294661A1/en not_active Abandoned
  • 2012-11-27 KR KR1020147017639A patent/KR20140117370A/ko not_active Application Discontinuation
  • 2012-11-27 IN IN959KON2014 patent/IN2014KN00959A/en unknown
  • 2012-11-27 JP JP2013546991A patent/JP5713118B2/ja active Active
  • 2012-11-27 CN CN201280059270.9A patent/CN103975086B/zh active Active
  • 2012-11-29 TW TW101144674A patent/TWI519652B/zh active

Patent Citations (3)

Also Published As

Similar Documents

Legal Events