WO2018003521A1 - フェライト系ステンレス鋼板 - Google Patents
フェライト系ステンレス鋼板 Download PDFInfo
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- WO2018003521A1 WO2018003521A1 PCT/JP2017/022134 JP2017022134W WO2018003521A1 WO 2018003521 A1 WO2018003521 A1 WO 2018003521A1 JP 2017022134 W JP2017022134 W JP 2017022134W WO 2018003521 A1 WO2018003521 A1 WO 2018003521A1
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- C—CHEMISTRY; METALLURGY
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- 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
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- 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
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- 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
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
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- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Definitions
- the present invention relates to a ferritic stainless steel sheet.
- the present invention relates to a ferritic stainless steel sheet that has an excellent weld shape.
- it is related also with the ferritic stainless steel plate excellent in the surface property of the weld part after a process.
- Ferritic stainless steel sheets are used for many purposes because they are cheaper than austenitic stainless steel sheets containing a lot of expensive Ni.
- ferritic stainless steel sheets are used in a wide range of fields such as home appliances, kitchen equipment, building members, building hardware, and structural members.
- a stainless steel plate may be formed into a member having a predetermined shape by pressing, and a plurality of members may be assembled and used by welding.
- welding is important, and the shape of the weld is particularly important. For example, if there is a shape defect such as an undercut in the welded part, it may become a starting point of joint strength reduction or crack generation or fatigue failure due to stress concentration, so appropriate measures are required.
- shape of the welded part is also important for members that are used after being welded.
- scoring polishing removal of the temper collar by polishing
- the welded parts are also required to have corrosion resistance.
- the welding may be not only the same material welding but also a different material welding with the austenitic stainless steel plate, and it is necessary to ensure the corrosion resistance of not only the same material welding part but also the different material welding part.
- the penetration depth is adjusted by controlling the content of O, Al, Si, and Mn in low Cr-containing Ti and V-added steel, and the ductility of the welded portion is ensured.
- a method is disclosed.
- Patent Document 2 discloses a method of improving corrosion resistance by adding Nb and suppressing Cr carbonitride precipitation.
- Patent Document 3 discloses a technique for optimizing the contents of Al, Ti, Si, and Ca, suppressing the amount of black spots generated in a TIG weld, and improving the corrosion resistance and workability of the weld.
- JP-A-8-170154 Japanese Patent No. 5205951 Japanese Patent No. 5487759
- Conventional ferritic stainless steel sheets may not have a good weld shape in various applications such as cooking utensils, combustion equipment processed parts, refrigerator front doors, battery cases, and construction hardware. Moreover, the corrosion resistance of a favorable dissimilar material welded part may not be obtained.
- the present invention intends to provide a ferritic stainless steel sheet that is excellent in welded part shape and excellent in corrosion resistance of a dissimilar welded part with austenitic stainless steel.
- the present inventors have conducted intensive studies on the chemical composition of steel affecting the welded part shape and the corrosion resistance of the welded part.
- the contained elements by specifying the contained elements and optimizing the content balance of Nb, Ti, Zr, Si, Al, it is possible to improve the shape of the welded part and to suppress the deterioration of the corrosion resistance of the dissimilar material welded part.
- the inventors of the present invention have made further investigations on the influence of the chemical composition of steel on the surface properties after processing such as forming a welded part. As a result, it has been found that the deterioration of the surface properties after processing such as forming in the welded portion can be suppressed by defining the component composition and optimizing the composite content of Ti, Nb, Zr, and Al.
- processing in the welded portion may be simply referred to as “processing in the welded portion”.
- the present inventors have further studied and completed the present invention.
- the gist of the present invention is as follows.
- the ferritic stainless steel sheet of the present invention can form an excellent welded part shape, and can greatly improve the corrosion resistance of a dissimilar welded part with austenitic stainless steel as compared with a conventional material.
- the ferritic stainless steel sheet of the present invention can greatly improve the surface properties after processing of the welded portion as compared with the conventional material. That is, the ferritic stainless steel sheet of the present invention can remarkably reduce the deterioration of surface properties in a member that requires designability after processing.
- the ferritic stainless steel sheet according to the present invention can remarkably improve the characteristics of the product, and has a remarkable industrial effect.
- FIG. 1 is an observation example of a cross-sectional shape of a TIG welded portion in the example.
- the right side is a ferritic stainless steel plate and the left side is a SUS304 steel plate.
- Each observation example with dripping (A), with undercut (B), and excellent weld shape (C) is shown.
- the C content is set to 0.020% or less.
- the C content is preferably 0.015% or less.
- excessive steel content reduction increases steelmaking costs, so the lower limit of C content is 0.003%.
- the C content is preferably 0.005% or more.
- C is a solid solution strengthening element having an effect of suppressing the grain growth of recrystallized grains.
- the content of C is excessively small, the crystal grain size of the welded part becomes coarse, and the surface after processing of the welded part Causes deterioration of properties. Therefore, in order to improve the surface properties after processing of the welded portion, it is necessary to contain 0.003% or more of C.
- the C content is preferably 0.005% or more.
- Si 0.01 to 1.00% Si contributes to deoxidation of steel, but the effect cannot be obtained if the Si content is less than 0.01%. Therefore, the Si content is 0.01% or more.
- the Si content is preferably 0.05% or more, and more preferably 0.10% or more.
- Si content becomes like this. Preferably it is 0.50% or less, More preferably, it is 0.25% or less.
- Si is a solid solution strengthening element that has the effect of suppressing the grain growth of recrystallized grains.
- the Si content is excessively small, the crystal grain size of the welded part becomes coarse, and the surface after processing of the welded part Causes deterioration of properties. Therefore, when improving the surface property after processing of a welded part, the content of Si of 0.03% or more is preferable.
- the Si content is more preferably 0.05% or more.
- Mn 0.01 to 0.50% Since Mn forms MnS and adversely affects the corrosion resistance, the Mn content is 0.50% or less.
- the Mn content is preferably 0.30% or less, more preferably 0.25% or less.
- Mn is a solid solution strengthening element, and the solid solution Mn present in the steel in the welded portion contributes to the strength and has the effect of suppressing the sag of the welded molten portion and obtaining an excellent welded portion shape.
- the Mn content is 0.01% or more.
- the Mn content is preferably 0.05% or more, more preferably 0.10% or more.
- Mn is a solid solution strengthening element having an effect of suppressing the grain growth of recrystallized grains. If the content of Mn is excessively small, the crystal grain size of the welded part becomes coarse, and the surface after processing of the welded part Causes deterioration of properties. Therefore, when improving the surface property after processing of a welded part, the content of Mn of 0.03% or more is preferable. The Mn content is more preferably 0.05% or more.
- P 0.040% or less If P is contained in excess of 0.040%, the corrosion resistance is adversely affected, so the P content is 0.040% or less.
- the P content is preferably 0.030% or less. The lower the P content, the better. The lower limit is not particularly defined.
- the content of S is preferably as small as possible. Therefore, in the present invention, the S content is set to 0.010% or less. S content becomes like this. Preferably it is 0.0050% or less, More preferably, it is 0.0040% or less. The lower the S content, the better. The lower limit is not particularly defined.
- Cr 20.0 to 24.0% Cr is an element that improves the corrosion resistance, and is an indispensable element in ferritic stainless steel sheets. Since such an effect becomes remarkable when the Cr content is 20.0% or more, the Cr content is 20.0% or more. The Cr content is preferably 20.5% or more. On the other hand, when the Cr content exceeds 24.0%, the elongation is significantly reduced. Therefore, the Cr content is 24.0% or less. The Cr content is preferably 22.0% or less, more preferably 21.5% or less.
- Cu 0.20 to 0.80% Cu contributes to the improvement of corrosion resistance. Further, the solid solution Cu present in the steel in the welded portion contributes to the strength, and has an effect of suppressing the sag of the welded molten portion and obtaining an excellent welded portion shape. This effect is exhibited when 0.20% or more of Cu is contained. Therefore, the Cu content is 0.20% or more. The Cu content is preferably 0.30% or more, and more preferably 0.40% or more. On the other hand, if Cu is contained excessively, the elongation decreases, so the Cu content is set to 0.80% or less. The Cu content is preferably 0.60% or less, more preferably 0.50% or less.
- Ni 0.01 to 0.60% Ni contributes to the improvement of corrosion resistance, and exhibits an effect when contained in an amount of 0.01% or more. Therefore, the Ni content is 0.01% or more.
- the Ni content is preferably 0.05% or more, more preferably 0.10% or more.
- the Ni content exceeds 0.60%, the elongation decreases, so the Ni content is 0.60% or less.
- the Ni content is preferably 0.40% or less.
- Al 0.01 to 0.08% Al contributes to deoxidation of the steel, but if less than 0.01%, the effect cannot be obtained. Therefore, the Al content is 0.01% or more. On the other hand, when Al is contained excessively exceeding 0.08%, a large amount of Al oxide is generated at the time of welding, and this Al oxide is caught in the weld melted part, which adversely affects the corrosion resistance of the welded part. For this reason, the upper limit of the Al content is set to 0.08%.
- the Al content is preferably 0.06% or less, and more preferably 0.05% or less. More preferably, it is 0.04% or less.
- Al is an element that suppresses the grain growth of the crystal grain of the welded portion by the pinning effect of the Al-based precipitate, and when contained in an amount of 0.01% or more, the effect of improving the surface properties after processing of the welded portion is exhibited. To do. Therefore, when improving the surface property after processing of the welded portion, the Al content is set to 0.01% or more. The Al content is preferably 0.02% or more. On the other hand, when Al is contained excessively, Al inclusions are unevenly distributed in the welded portion, and the grain growth of crystal grains becomes uneven. As a result, a non-uniform structure in which coarse crystal grains and fine crystal grains are mixed is formed, and the surface properties after processing of the welded portion deteriorate. For this reason, when improving the surface property after processing of a welded part, the upper limit of Al content was made into 0.08%. The Al content is preferably 0.06% or less.
- N 0.003 to 0.020% Since N causes a decrease in the corrosion resistance of the weld due to sensitization, the lower the N content, the better. Therefore, in the present invention, the N content is set to 0.020% or less.
- the N content is preferably 0.015% or less.
- the lower limit of the N content was set to 0.003%.
- the amount of N is preferably 0.005% or more.
- N is a solid solution strengthening element having an effect of suppressing the grain growth of recrystallized grains.
- the content of N is excessively small, the crystal grain size of the welded part becomes coarse, and the surface after processing of the welded part Causes deterioration of properties. Therefore, in order to improve the surface properties after processing of the welded portion, it is necessary to contain 0.003% or more of N.
- the N content is preferably 0.005% or more.
- Nb 0.40 to 0.80%
- Nb is a carbonitride-forming element, fixes C and N, and suppresses a decrease in corrosion resistance of the weld due to sensitization.
- the solid solution Nb present in the steel in the welded portion contributes to the strength, and has the effect of suppressing the sag of the welded molten portion and obtaining an excellent welded portion shape. The said effect is exhibited when Nb is contained 0.40% or more. Therefore, the Nb content is 0.40% or more.
- the Nb content is preferably 0.45% or more, more preferably 0.50% or more.
- the Nb content is 0.80% or less.
- the Nb content is preferably 0.75% or less, and more preferably 0.70% or less.
- Nb can suppress the grain growth of crystal grains in the weld due to the pinning effect of Nb-based precipitates. These effects are exhibited when Nb is contained in an amount of 0.40% or more. Therefore, when improving the surface properties after processing the welded portion, the Nb content is 0.40% or more, preferably 0.55% or more.
- Ti 0.01 to 0.10% Ti, like Nb, is a carbonitride-forming element, fixes C and N, and suppresses a decrease in corrosion resistance due to sensitization.
- the solid solution Ti present in the steel in the welded portion contributes to the strength, and has the effect of suppressing the sag of the welded molten portion and obtaining an excellent welded portion shape. The said effect is exhibited when 0.01% or more of Ti is contained. Therefore, the Ti content is 0.01% or more.
- the Ti content is preferably 0.05% or less.
- the Ti content is more preferably 0.04% or less.
- Ti is an element that suppresses the grain growth of the weld due to the pinning effect of Ti-based precipitates.
- the Ti content is set to 0.01% or more.
- the Ti content is preferably 0.02% or more.
- Ti-based inclusions are locally unevenly distributed in the welded portion, and the grain growth of crystal grains becomes uneven.
- the Ti content is set to 0.10% or less.
- the Ti content is preferably 0.08% or less, and more preferably 0.06% or less.
- the Ti content is more preferably 0.04% or less.
- Zr 0.01 to 0.10%
- Zr is a carbonitride-forming element like Nb and Ti, fixes C and N, and suppresses a decrease in corrosion resistance of the weld due to sensitization.
- the solid solution Zr present in the steel in the welded portion contributes to the strength, and has an effect of suppressing the sag of the welded molten portion and obtaining an excellent welded portion shape. The said effect is exhibited when 0.01% or more of Zr is contained. Therefore, the Zr content is 0.01% or more.
- the Zr content is if the Zr content exceeds 0.10%, surface defects caused by inclusions are caused, so the upper limit of the Zr content is 0.10%.
- the Zr content is preferably 0.05% or less.
- Zr is an important element for ensuring good surface properties of the weld. Zr precipitates finely in the cooling process from the time of solidification in the weld melt, and suppresses coarsening of crystal grains. Thereby, Zr contributes to ensuring the surface property of the favorable weld part after a process. From the viewpoint of obtaining this effect, the Zr content is set to 0.01% or more. The Zr content is preferably 0.02% or more. On the other hand, if Zr is excessively contained, Zr-based inclusions are unevenly distributed in the welded portion, and the grain growth of the crystal grains becomes non-uniform, and a non-uniform structure in which coarse crystal grains and fine crystal grains are mixed is formed. .
- the Zr content was set to 0.10% or less.
- the Zr content is preferably 0.08% or less, and more preferably 0.06% or less.
- Ti and Zr are elements that form carbonitrides in steel and improve the corrosion resistance of dissimilar welds with austenitic stainless steel. Therefore, from the viewpoint of securing the welded portion corrosion resistance, it is preferable to contain a certain amount of Ti and Zr. Furthermore, by using Zr and Ti together instead of adding Ti or Zr alone, it is possible to suppress the formation of coarse Ti-based precipitates by the formation of Zr-based precipitates, and the precipitates can be finely dispersed in the weld metal. Thus, good corrosion resistance can be ensured.
- Nb is also important and needs to be contained in a predetermined amount. In particular, in order to ensure the unprecedented excellent corrosion resistance of the dissimilar welded portion, Nb that forms carbide after Zr and Ti is important in the process of cooling and solidifying the welded molten metal.
- composition of the basic component has been described above, the present invention may further contain the following elements.
- V 0.01 to 0.30%
- V is a carbonitride-forming element, and suppresses a decrease in corrosion resistance of the weld due to sensitization.
- the V content is preferably 0.01% or more.
- the upper limit of V content is preferably 0.30%.
- the V content is more preferably 0.20% or less.
- Mo 0.01-0.30% Mo is effective in improving the corrosion resistance.
- the solid solution Mo which exists in steel in a welding part contributes to an intensity
- the Mo content is preferably 0.01% or more.
- the Mo content is preferably 0.30% or less.
- the Mo content is more preferably 0.20% or less, and still more preferably 0.15% or less.
- Co 0.01 to 0.30% Co is effective in improving the corrosion resistance. Further, the solid solution Co present in the steel in the welded portion contributes to the strength, and has an effect of suppressing the sag of the welded molten portion and obtaining an excellent welded portion shape. From the viewpoint of obtaining the above effects, the Co content is preferably 0.01% or more. On the other hand, if the Co content is excessive, the elongation decreases, so the Co content is preferably 0.30% or less. The Co content is more preferably 0.20% or less, and still more preferably 0.15% or less.
- B 0.0003 to 0.0050%
- B is an element that improves hot workability and secondary workability. From the viewpoint of obtaining this effect, the B content is preferably 0.0003% or more. The B content is more preferably 0.0010% or more. If the B content exceeds 0.0050%, the toughness may decrease. Therefore, the B content is preferably 0.0050% or less. The B content is more preferably 0.0030% or less.
- Ca 0.0003 to 0.0050%
- Ca is an element effective for deoxidation, and from the viewpoint of obtaining this effect, the Ca content is preferably 0.0003% or more.
- the Ca content is more preferably 0.0005% or more. If the Ca content exceeds 0.0050%, the corrosion resistance may decrease. Therefore, the Ca content is preferably 0.0050% or less.
- the Ca content is more preferably 0.0020% or less.
- Mg acts as a deoxidizer. From the viewpoint of obtaining this effect, the Mg content is preferably 0.0005% or more. The Mg content is more preferably 0.0010% or more. If the Mg content exceeds 0.0050%, the toughness of the steel is lowered and the productivity may be lowered. Therefore, the Mg content is preferably 0.0050% or less. The Mg content is more preferably 0.0030% or less.
- REM (rare earth metal): 0.001 to 0.050% REM (rare earth metal: elements having atomic numbers 57 to 71 such as La, Ce, and Nd) is an element that improves high-temperature oxidation resistance. From the viewpoint of obtaining this effect, the REM content is preferably 0.001% or more. The REM content is more preferably 0.005% or more. If the REM content exceeds 0.050%, surface defects may occur during hot rolling. Therefore, the REM content is preferably 0.050% or less. The REM content is more preferably 0.030% or less.
- Sn 0.01 to 0.50% Sn is effective for suppressing roughening of the work surface by promoting the generation of deformation bands during rolling. From the viewpoint of obtaining this effect, the Sn content is preferably 0.01% or more. The Sn content is more preferably 0.03% or more. If the Sn content exceeds 0.50%, the workability may decrease. Therefore, the Sn content is preferably 0.50% or less. The Sn content is more preferably 0.20% or less.
- Sb 0.01 to 0.50% Similar to Sn, Sb is effective in suppressing roughening of the processed skin by promoting deformation band generation during rolling. From the viewpoint of obtaining this effect, the Sb content is preferably 0.01% or more. The Sb content is more preferably 0.03% or more. If the Sb content exceeds 0.50%, the workability may decrease. Therefore, the Sb content is preferably 0.50% or less. The Sb content is more preferably 0.20% or less.
- the balance is Fe and inevitable impurities.
- each component merely satisfies the above component composition range, and the relationship of the following formula (1) must also be satisfied.
- the element symbol in Formula (1) represents content (mass%) of the element. 3.0 ⁇ Nb / (2Ti + Zr + 0.5Si + 5Al) ⁇ 1.5 (1)
- the above formula (1) is for obtaining an excellent welded part shape free from shape defects such as sagging and undercut in the welded melt part by optimizing the content balance of Nb, Ti, Zr, Si, and Al. This is a necessary condition.
- the coefficient of the above formula (1) is obtained experimentally.
- undercutting may occur at the boundary between the austenitic stainless steel plate and the molten metal during welding of different materials. Therefore, in order to obtain an excellent welded portion shape, it is preferable to have a content balance in which the total content of Ti, Zr, Si, and Al is small and the Nb content is large. Generation
- production of the shape defect of a welded part will become remarkable as the value of Formula (1) is less than 1.5. On the other hand, when the value of the formula (1) is 1.5 or more, the welded portion shape is excellent. Therefore, the value of the formula (1) is 1.5 or more.
- the value of formula (1) is preferably 1.6 or more.
- the value of the formula (1) is more than 3.0, the occurrence of a defective shape of the welded portion becomes remarkable.
- the value of the formula (1) is 3.0 or less, the welded portion shape is excellent. Therefore, the value of Formula (1) is set to 3.0 or less.
- the value of formula (1) is preferably 2.9 or less, more preferably 2.8 or less.
- the element symbol in Formula (2) represents content (mass%) of the element.
- the above formula (2) is useful from the viewpoint of obtaining good surface properties in the welded portion after processing.
- the value obtained from the above formula (2) is less than 0.75, the surface properties of the welded portion after processing are not sufficiently improved.
- the value obtained from the formula (2) is 0.75 or more, the surface property of the welded portion after processing is excellent.
- the value obtained from the formula (2) is preferably 0.80 or more.
- the upper limit of the value obtained from the formula (2) is preferably 1.00 from the viewpoint of suppressing excessive hardening and ensuring good elongation.
- Ti, Nb, Zr, and Al can be precipitated in the steel as carbonitrides and oxides. Precipitates improve the structure uniformity of the weld due to the pinning effect.
- the following defects can occur in the weld-melted portion in the steel with Ti alone added. That is, a Ti-based precipitate that starts to precipitate from a high temperature and is coarsened and a fine Ti-based precipitate that precipitates at a low temperature during cooling are mixed. Aggregated and coarsened Ti-based precipitates and fine Ti-based precipitates have different effects on grain growth, resulting in a mixed grain structure in which coarse and fine grains are mixed and non-uniform in crystal grain size. Surface properties after processing deteriorate.
- Nb precipitates at a lower temperature than Ti. For this reason, the pinning effect by the fine Nb-based precipitate is expected in a temperature range lower than the Ti precipitation start temperature range. However, a pinning effect due to precipitates cannot be expected in a high temperature region where Nb has not yet been precipitated, and a certain amount of coarse crystal grains are generated, resulting in deterioration of the surface properties of the welded portion after processing.
- Zr single added steel also precipitates from high temperature like Ti. For this reason, similarly to the Ti-added steel, the Zr-added steel also has a mixed grain structure in which coarse and fine grains are mixed, and the surface properties after processing of the welded portion deteriorate.
- AlAl-added steel also precipitates at a lower temperature than Ti, as does Nb-added steel. For this reason, the Al-added steel cannot be expected to have a pinning effect due to precipitates in a high temperature region, and a certain amount of coarse crystal grains are generated, and the surface properties after processing of the welded portion deteriorate.
- the welded portion has a non-uniform mixed grain structure, there are regions with many crystal grain boundaries and regions with few. In this case, strain introduced by processing is unevenly distributed in the crystal grain boundaries or part of the crystal grains, and uniform deformation cannot be achieved, making it difficult to achieve good surface properties.
- the ferritic stainless steel sheet according to the present invention is suitable for use in which processing such as tension processing, bending processing, drawing processing, and overhang processing is performed.
- the thickness of the steel plate is not particularly limited, but can usually be 0.10 to 6.0 mm.
- the ferritic stainless steel sheet of this invention is suitable for the use welded.
- the welding conditions are not particularly limited and may be determined as appropriate.
- the welding is preferably TIG welding.
- a welded member in which a ferritic stainless steel plate and an austenitic stainless steel plate are combined is manufactured by TIG welding. Therefore, this TIG welding can also be a manufacturing method of the welding member of the present invention.
- the welding conditions for TIG welding may be appropriately determined, and preferable conditions are as follows.
- Welding voltage 8-15V
- Welding current 50-250A
- Welding speed 100 to 1000 mm / min
- Electrode 1-5mm ⁇ tungsten electrode
- SUS304, SUS304L, SUS316, SUS316L etc. are preferable, for example.
- SUS304 is used. Because SUS304 has similar weldability to other three austenitic stainless steel types, it is reasonable that the effect of the present invention obtained by using SUS304 can be obtained by using other austenitic stainless steel plates. Guessed.
- the ferritic stainless steel sheet of the present invention may be used for welding of homogeneous materials, and is a heterogeneous material such as austenitic stainless steel, martensitic stainless steel, precipitation stainless steel, and two-phase stainless steel. It may be used for welding with stainless steel.
- the method for producing the ferritic stainless steel sheet of the present invention is not particularly limited. Hereinafter, a suitable production method for the ferritic stainless steel sheet of the present invention, particularly a cold-rolled sheet, will be described.
- the steel having the above component composition is melted by a known method such as a converter, electric furnace, vacuum melting furnace or the like, and further subjected to secondary refining by a VOD (vacuum oxygen decarburization) method or the like. Thereafter, a steel material (slab) is obtained by a continuous casting method or an ingot-bundling method. This steel material is heated to 1000 ° C. to 1250 ° C., and then hot-rolled to a plate thickness of 2.0 mm to 8.0 mm under a finishing temperature of 700 ° C. to 1050 ° C. The hot-rolled sheet thus prepared is annealed at a temperature of 850 ° C. to 1100 ° C.
- cold-rolled and cold-rolled sheet is annealed at a temperature of 800 ° C. to 1050 ° C.
- pickling is performed to remove scale.
- Skin pass rolling may be performed on the cold-rolled sheet from which the scale has been removed.
- Specimens (rolling direction (L direction) 200 mm ⁇ vertical direction (C direction) 90 mm) were collected from each steel plate obtained as described above. The thickness of the test piece was measured under the TIG welding conditions of welding voltage: 10 V, welding current: 90 to 110 A, welding speed: 600 mm / min, electrode: 1.6 mm ⁇ tungsten electrode, front and back shield gas (Ar gas) 20 L / min. Butt weld joints were made with 1.0 mm SUS304 (rolling direction 200 mm ⁇ 90 mm perpendicular to the rolling direction) and 200 mm sides. Therefore, the welding direction (the direction of the weld bead) is parallel to the rolling direction.
- a welded part is a welded molten metal part and a welded heat affected part.
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Abstract
Description
C:0.003~0.020%、
Si:0.01~1.00%、
Mn:0.01~0.50%、
P:0.040%以下、
S:0.010%以下、
Cr:20.0~24.0%、
Cu:0.20~0.80%、
Ni:0.01~0.60%、
Al:0.01~0.08%、
N:0.003~0.020%、
Nb:0.40~0.80%、
Ti:0.01~0.10%、
Zr:0.01~0.10%、
を含有し、残部がFeおよび不可避的不純物からなり、下記式(1)を満足する、フェライト系ステンレス鋼板。
3.0≧Nb/(2Ti+Zr+0.5Si+5Al)≧1.5・・・(1)
なお、式(1)における元素記号は、その元素の含有量(質量%)をあらわす。
2Ti+Nb+1.5Zr+3Al≧0.75・・・(2)
なお、式(2)における元素記号は、その元素の含有量(質量%)をあらわす。
Mo:0.01~0.30%、
Co:0.01~0.30%
の1種以上を含有する、[1]から[3]のいずれかに記載のフェライト系ステンレス鋼板。
B:0.0003~0.0050%、
Ca:0.0003~0.0050%、
Mg:0.0005~0.0050%、
REM:0.001~0.050%、
Sn:0.01~0.50%、
Sb:0.01~0.50%
の1種以上を含有する、[1]から[4]のいずれかに記載のフェライト系ステンレス鋼板。
Cは鋭敏化に起因する溶接部の耐食性の低下の原因となるため、C含有量は低いほど好ましい。そこで、本発明では、C含有量を0.020%以下とする。C含有量は、好ましくは0.015%以下である。一方、過度のC含有量低減は製鋼コストが増加するため、C含有量の下限を0.003%とする。C含有量は、好ましくは0.005%以上である。
Siは鋼の脱酸に寄与するが、Si含有量が0.01%未満ではその効果は得られない。よって、Si含有量は0.01%以上とする。Si含有量は、好ましくは0.05%以上であり、より好ましくは0.10%以上である。一方、Siを1.00%を超えて過剰に含有すると溶接時にSi酸化物を多量に生成し、溶接溶融部に巻き込まれ、溶接部の耐食性に悪影響を及ぼす。また、Si含有量が多くなると鋼が硬質化して加工性が低下する。よってSi含有量は1.00%以下とする。Si含有量は、好ましくは0.50%以下であり、より好ましくは0.25%以下である。
MnはMnSを形成し耐食性に悪影響を及ぼすため、Mn含有量は0.50%以下とする。Mn含有量は、好ましくは0.30%以下であり、より好ましくは0.25%以下である。
Pを0.040%を超えて含有すると耐食性に悪影響を及ぼすため、P含有量は0.040%以下とする。P含有量は、好ましくは0.030%以下である。P含有量は低いほど好ましく、下限は特に規定しない。
Sは、MnS介在物を形成し、耐食性に悪影響を及ぼすため、Sの含有量は少ないほど好ましい。そこで、本発明では、S含有量を0.010%以下とする。S含有量は、好ましくは0.0050%以下であり、より好ましくは0.0040%以下である。S含有量は低いほど好ましく、下限は特に規定しない。
Crは、耐食性を向上させる元素であり、フェライト系ステンレス鋼板では不可欠の元素である。このような効果はCr含有量20.0%以上の含有で顕著となるため、Cr含有量は20.0%以上とする。Cr含有量は、好ましくは20.5%以上である。一方、Cr含量が24.0%を超えると、伸びが顕著に低下する。よって、Cr含有量は24.0%以下とする。Cr含有量は、22.0%以下が好ましく、より好ましくは21.5%以下である。
Cuは耐食性の向上に寄与する。また溶接部において鋼中に存在する固溶Cuは強度に寄与し、溶接溶融部の垂れを抑制し優れた溶接部形状を得る効果を有する。Cuを0.20%以上含有するとこの効果を発揮する。よって、Cu含有量は0.20%以上とする。Cu含有量は、好ましくは0.30%以上とし、より好ましくは0.40%以上である。一方、Cuを過度に含有すると、伸びが低下するため、Cu含有量を0.80%以下とする。Cu含有量は、好ましくは0.60%以下であり、より好ましくは0.50%以下である。
Niは、耐食性の向上に寄与し、0.01%以上含有すると効果を発揮する。よって、Ni含有量は0.01%以上とする。Ni含有量は、好ましくは0.05%以上であり、より好ましくは0.10%以上である。一方で、Niを0.60%を超えて過剰に含有すると、伸びが低下するため、Ni含有量は0.60%以下とする。Ni含有量は、好ましくは0.40%以下である。
Alは鋼の脱酸に寄与するが、0.01%未満ではその効果は得られない。よって、Al含有量は0.01%以上とする。一方、Alを0.08%を超えて過度に含有すると溶接時にAl酸化物を多量に生成し、このAl酸化物が溶接溶融部に巻き込まれ、溶接部の耐食性に悪影響を及ぼす。このため、Al含有量の上限を0.08%とする。Al含有量は、好ましくは0.06%以下であり、より好ましくは0.05%以下である。さらに好ましくは0.04%以下である。
Nは鋭敏化に起因する溶接部の耐食性の低下の原因となるため、N含有量は低いほど好ましい。そこで、本発明では、N含有量を0.020%以下とする。N含有量は、好ましくは0.015%以下である。一方、Nの過度の低減は製鋼コストが増加するため、N含有量の下限を0.003%とした。N量は、好ましくは0.005%以上である。
Nbは、炭窒化物形成元素であり、C、Nを固定し、鋭敏化に起因する溶接部の耐食性の低下を抑制する。また、溶接部において鋼中に存在する固溶Nbは強度に寄与し、溶接溶融部の垂れを抑制し優れた溶接部形状を得る効果を有する。上記効果は、Nbを0.40%以上含有すると発揮される。よって、Nb含有量は0.40%以上とする。Nb含有量は、好ましくは0.45%以上であり、より好ましくは0.50%以上である。一方、過剰にNbを含有すると伸びを低下させるため、Nb含有量は0.80%以下とする。Nb含有量は、好ましくは0.75%以下であり、より好ましくは0.70%以下である。
Tiは、Nb同様に炭窒化物形成元素であり、C、Nを固定し、鋭敏化に起因する耐食性の低下を抑制する。また、溶接部において鋼中に存在する固溶Tiは強度に寄与し、溶接溶融部の垂れを抑制し優れた溶接部形状を得る効果を有する。上記効果はTiを0.01%以上含有すると発揮される。よって、Ti含有量は0.01%以上とする。一方、Tiを0.10%を超えて含有すると介在物に起因する表面欠陥をもたらすため、上限を0.10%とする。Ti含有量は、好ましくは0.05%以下である。Ti含有量は、さらに好ましくは0.04%以下である。
Zrは、Nb、Ti同様に炭窒化物形成元素であり、C、Nを固定し、鋭敏化に起因する溶接部の耐食性の低下を抑制する。また、溶接部において鋼中に存在する固溶Zrは強度に寄与し、溶接溶融部の垂れを抑制し優れた溶接部形状を得る効果を有する。上記効果はZrを0.01%以上含有すると発揮される。よって、Zr含有量は0.01%以上とする。一方、Zrを0.10%を超えて含有すると介在物に起因する表面欠陥をもたらすため、Zr含有量の上限を0.10%とした。Zr含有量は、好ましくは0.05%以下である。
Vは、炭窒化物形成元素であり、鋭敏化に起因する溶接部の耐食性の低下を抑制する。この効果を得る観点から、V含有量は0.01%以上が好ましい。一方、Vを過剰に含有すると加工性が低下するためV含有量の上限は0.30%が好ましい。V含有量は、より好ましくは0.20%以下である。
Moは耐食性の向上に有効である。また、溶接部において鋼中に存在する固溶Moは強度に寄与し、溶接溶融部の垂れを抑制し優れた溶接部形状を得る効果を有する。上記効果を得る観点から、Mo含有量は0.01%以上が好ましい。一方、Moを過度に含有すると、伸びが低下するため、Mo含有量は0.30%以下が好ましい。Mo含有量は、より好ましくは0.20%以下であり、さらに好ましくは0.15%以下である。
Coは耐食性の向上に有効である。また、溶接部において鋼中に存在する固溶Coは強度に寄与し、溶接溶融部の垂れを抑制し優れた溶接部形状を得る効果を有する。上記効果を得る観点から、Co含有量は0.01%以上が好ましい。一方、Coを過度に含有すると、伸びが低下するため、Co含有量は0.30%以下が好ましい。Co含有量は、より好ましくは0.20%以下であり、さらに好ましくは0.15%以下である。
Bは、熱間加工性や2次加工性を向上させる元素であり、この効果を得る観点から、B含有量は0.0003%以上が好ましい。B含有量はより好ましくは0.0010%以上である。B含有量が0.0050%を超えると靱性が低下するおそれがある。従って、B含有量は0.0050%以下が好ましい。B含有量はより好ましくは0.0030%以下である。
Caは、脱酸に有効な元素であり、この効果を得る観点から、Ca含有量は0.0003%以上が好ましい。Ca含有量はより好ましくは0.0005%以上である。Ca含有量が0.0050%を超えると耐食性が低下するおそれがある。従って、Ca含有量は0.0050%以下が好ましい。Ca含有量はより好ましくは0.0020%以下である。
Mgは脱酸剤として作用する。この効果を得る観点からMg含有量は0.0005%以上が好ましい。Mg含有量はより好ましくは0.0010%以上である。Mg含有量が0.0050%を超えると鋼の靱性が低下して製造性が低下するおそれがある。従って、Mg含有量は0.0050%以下が好ましい。Mg含有量は、より好ましくは0.0030%以下である。
REM(希土類金属:La、Ce、Ndなどの原子番号57~71の元素)は、耐高温酸化性を向上させる元素である。この効果を得る観点からREM含有量は0.001%以上が好ましい。REM含有量はより好ましくは0.005%以上である。REM含有量が0.050%を超えると、熱間圧延の際に表面欠陥が生じるおそれがある。よって、REM含有量は0.050%以下が好ましい。REM含有量はより好ましくは0.030%以下である。
Snは、圧延時における変形帯生成の促進による加工肌荒れ抑制に効果的である。この効果を得る観点から、Snの含有量は0.01%以上が好ましい。Snの含有量はより好ましくは0.03%以上である。Snの含有量が0.50%を超えると加工性が低下するおそれがある。よって、Sn含有量は0.50%以下が好ましい。Sn含有量はより好ましくは0.20%以下である。
Sbは、Snと同様に、圧延時における変形帯生成の促進による加工肌荒れ抑制に効果的である。この効果を得る観点から、Sb含有量は0.01%以上が好ましい。Sb含有量はより好ましくは0.03%以上である。Sbの含有量が0.50%を超えると加工性が低下するおそれがある。よって、Sb含有量は0.50%以下が好ましい。Sb含有量はより好ましくは0.20%以下である。
3.0≧Nb/(2Ti+Zr+0.5Si+5Al)≧1.5・・・(1)
上記式(1)は、Nb、Ti、Zr、Si、およびAlの含有量バランスを適正化することにより、溶接溶融部における垂れ、アンダーカットなどの形状不良のない優れた溶接部形状を得るために必要な条件である。上記式(1)の係数は実験的に求めている。
上記式(2)は、加工後の溶接部において良好な表面性状を得る観点から有用である。上記式(2)から求まる値が0.75未満であると、加工後における溶接部の表面性状が十分に向上しない。これに対して、式(2)から求まる値が0.75以上であると、加工後における溶接部の表面性状に優れたものとなる。式(2)から求まる値は、好ましくは0.80以上である。一方、過度な硬質化を抑制する観点、良好な伸びの確保の観点から、式(2)から求まる値の上限は1.00が好ましい。
溶接電圧:8~15V、
溶接電流:50~250A、
溶接速度:100~1000mm/min、
電極:1~5mmφタングステン電極、
表裏シールドガス(Arガス)5~40L/min
TIG溶接に用いられる前記オーステナイト系ステンレス鋼板として、例えば、SUS304、SUS304L、SUS316、SUS316Lなどが好ましい。後述の実施例ではSUS304を使用している。SUS304は他のオーステナイト系ステンレス3鋼種と溶接性が類似しているという理由から、SUS304を使用して得られた本発明の効果は他のオーステナイト系ステンレス鋼板を使用しても得られると合理的に推測される。
上記のようにして得られた各突合せ溶接継手から、試験片の長さ方向が溶接方向に平行かつ溶接ビードが幅方向の中心に位置するように板厚1.0mm×幅15mm×長さ10mmの試験片を採取し、王水エッチングし、溶接方向に垂直な断面観察実施した。突合せた左右の母材の位置より0.15mm以上溶接溶融部が低い箇所がある場合、垂れあり、と判定した(図1(A)「垂れ」参照)。また、母材に接する部分の溶接溶融部の厚みが母材の板厚より0.15mm以上薄い箇所がある場合をアンダーカットあり、と判定した(図1(B)「アンダーカットあり」参照)。垂れあり、またはアンダーカットありに該当した場合、溶接部形状不良「×」と判定した。一方、溶接部形状不良に該当しないものを溶接部形状良好「○」と判定した(図1「溶接部形状に優れる」参照)。結果を表1~3「溶接部形状」欄に示す。
試験片の長さ方向が溶接方向に平行かつ試験片の幅方向の中心線全長に溶接ビードが位置するように板厚1.0mm×幅60mm×長さ80mmの試験片を各突合せ溶接継手から採取し、♯600番の研磨紙で表面(溶接時の電極側)を表面研磨し、裏面の全面および試験片外周端部の幅5mmをシールにて被覆後、塩水噴霧(35℃、5%NaCl、2時間)、乾燥(60℃、4時間)、湿潤(50℃、4時間)を1サイクルとする複合サイクル腐食試験を30サイクル実施し、溶接ビード部を中心にして幅20mmの表面の部分の発銹面積率を測定した。発銹面積率が10%以下の場合を溶接部の耐食性良好「○」と判定した。発銹面積率が10%超えの場合を溶接部の耐食性不良「×」と判定した。結果を表1~3の「耐食性」欄に示す。
引張方向が溶接方向と直角かつ試験片の長さ方向の中心に溶接ビードが位置するようにJIS5号引張試験片を突合せ溶接継ぎ手から採取し、♯600番の研磨紙で表面研磨後、20%引張塑性歪を加え、溶接部の最大高さ粗さRzを溶接線方向に測定した。溶接部とは溶接溶融金属部と溶接熱影響部である。
Claims (5)
- 質量%で、
C:0.003~0.020%、
Si:0.01~1.00%、
Mn:0.01~0.50%、
P:0.040%以下、
S:0.010%以下、
Cr:20.0~24.0%、
Cu:0.20~0.80%、
Ni:0.01~0.60%、
Al:0.01~0.08%、
N:0.003~0.020%、
Nb:0.40~0.80%、
Ti:0.01~0.10%、
Zr:0.01~0.10%、
を含有し、残部がFeおよび不可避的不純物からなり、下記式(1)を満足する、フェライト系ステンレス鋼板。
3.0≧Nb/(2Ti+Zr+0.5Si+5Al)≧1.5・・・(1)
なお、式(1)における元素記号は、その元素の含有量(質量%)をあらわす。 - さらに、下記式(2)を満足する、請求項1に記載のフェライト系ステンレス鋼板。
2Ti+Nb+1.5Zr+3Al≧0.75・・・(2)
なお、式(2)における元素記号は、その元素の含有量(質量%)をあらわす。 - さらに、質量%で、V:0.01~0.30%を含む、請求項1または2に記載のフェライト系ステンレス鋼板。
- さらに、質量%で、
Mo:0.01~0.30%、
Co:0.01~0.30%
の1種以上を含有する、請求項1から3のいずれかに記載のフェライト系ステンレス鋼板。 - さらに、質量%で、
B:0.0003~0.0050%、
Ca:0.0003~0.0050%、
Mg:0.0005~0.0050%、
REM:0.001~0.050%、
Sn:0.01~0.50%、
Sb:0.01~0.50%
の1種以上を含有する、請求項1から4のいずれかに記載のフェライト系ステンレス鋼板。
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US16/310,956 US11220732B2 (en) | 2016-06-27 | 2017-06-15 | Ferritic stainless steel sheet |
ES17819881T ES2835273T3 (es) | 2016-06-27 | 2017-06-15 | Lámina de acero inoxidable ferrítico |
CN201780039942.2A CN109415784B (zh) | 2016-06-27 | 2017-06-15 | 铁素体系不锈钢板 |
EP17819881.8A EP3476961B1 (en) | 2016-06-27 | 2017-06-15 | Ferritic stainless steel sheet |
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EP3733910A4 (en) * | 2018-02-14 | 2020-11-04 | JFE Steel Corporation | FERRITIC STAINLESS STEEL |
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WO2021193479A1 (ja) * | 2020-03-25 | 2021-09-30 | 日鉄ステンレス株式会社 | 溶接構造、ステンレス鋼製溶接構造物、ステンレス鋼製溶接容器ならびにステンレス鋼 |
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