WO2023089693A1 - Feuille d'acier inoxydable ferritique - Google Patents

Feuille d'acier inoxydable ferritique Download PDF

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Publication number
WO2023089693A1
WO2023089693A1 PCT/JP2021/042235 JP2021042235W WO2023089693A1 WO 2023089693 A1 WO2023089693 A1 WO 2023089693A1 JP 2021042235 W JP2021042235 W JP 2021042235W WO 2023089693 A1 WO2023089693 A1 WO 2023089693A1
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Prior art keywords
stainless steel
ferritic stainless
less
steel sheet
content
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PCT/JP2021/042235
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English (en)
Japanese (ja)
Inventor
詠一朗 石丸
拓也 櫻庭
基 西村
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日鉄ステンレス株式会社
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Priority to KR1020247015162A priority Critical patent/KR20240073121A/ko
Priority to PCT/JP2021/042235 priority patent/WO2023089693A1/fr
Publication of WO2023089693A1 publication Critical patent/WO2023089693A1/fr

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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
    • 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
    • C21D8/0405—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 of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Definitions

  • the present invention relates to ferritic stainless steel sheets.
  • Ferritic stainless steel sheets are used in a wide range of fields such as home appliances, kitchen equipment, and electronic equipment, but their use has been limited due to their inferior formability compared to austenitic stainless steel.
  • improvements in refining technology have made it possible to make ferritic stainless steel extremely low in carbon and nitrogen.
  • Attempts have been made to increase corrosion resistance.
  • attempts have been made to improve the formability of ferritic stainless steels by controlling the chemical compositions and production methods, as in Patent Documents 1 to 3.
  • ferritic stainless steel Due to the improved formability of these conventional improvement technologies, ferritic stainless steel has come to be used in a wide range of applications. , further improvement is required. In other words, in order to reduce the weight of the final product, there is a demand for a ferritic stainless steel that is thinner than the conventional one and has higher formability.
  • bulging processing is a processing method in which the material is formed by plastic deformation, mainly elongation deformation of the part in contact with the punch, without flowing the material into the mold.
  • the deformation area is the area from the die shoulder to the punch head.
  • the contact load between the material and the punch is generally maximum around the punch shoulder, and the movement of the material is restricted, so deformation occurs between the punch shoulder and the die shoulder. is concentrated and the thickness reduction becomes the largest. And when a constriction occurs at this portion, it breaks.
  • Exterior panels for home appliances and kitchens are applications that particularly require members molded by this stretch molding.
  • such exterior panels were made of ordinary steel with a coating, but there was the problem of rusting at the edges and where the coating came off.
  • stainless steel has been widely used as a material for exterior panels for reasons such as the improvement of durability and the improvement of designability due to the clear coating that gives a luxurious appearance.
  • the exterior panel constitutes the appearance of the product, it is required to improve its dimensional accuracy. Therefore, processing such as stretch molding is often performed.
  • Patent Document 4 it has a predetermined chemical composition, a plate thickness of 0.4 to 0.8 mm, a molding speed of 3 to 10 mm / min, and an overhang height when an Erichsen test is performed.
  • a ferrite stainless steel plate for exterior panels having a thickness of 10 mm or more is described.
  • the molding speed is limited to 10 mm/min or less, and there is a certain limitation on the molding time required for the molded article. Therefore, there is a demand for further improvement in the productivity of molded products.
  • the present invention has been made in view of the above circumstances, and an object of the present invention is to provide a ferritic stainless steel sheet with excellent formability.
  • the present invention has the following configurations. [1] in % by mass, C: 0.0200% or less, Si: 0.70% or less, Mn: 1.00% or less, P: 0.030% or less, S: 0.005% or less, Cr: 11.0 to 19.5%, N: 0.020% or less, Al: 0.005 to 0.100%, O: 0.0050% or less, Ti: 0.03-0.20%, Nb: 0.010 to 0.300%, Sn: 0.001 to 0.300%, Zr: containing 0.001 to 0.080%,
  • the balance consists of iron and impurities, A ferritic stainless steel sheet having a chemical composition satisfying the following formulas (1) and (2), having a thickness of 1.0 mm or less, and having a critical drawing ratio in cylindrical deep drawing of 2.30 or more.
  • the ferritic stainless steel sheet according to claim 1 or 2 characterized by containing two or more kinds.
  • the average Lankford value is 1.8 or more, and the in-plane anisotropy ( ⁇ r) of the Lankford value is 0.5 or more.
  • a ferritic stainless steel sheet with excellent formability can be provided.
  • the ferritic stainless steel sheet according to the present invention can be used as a blank when manufacturing a thin-walled molded product that is required as a part for weight reduction of home electric appliances and kitchen equipment. , good moldability can be exhibited, so that a molded product satisfying dimensional accuracy and design can be obtained.
  • ferritic stainless steel sheets which are generally said to have lower formability than austenitic stainless steel sheets, and to obtain molded articles with excellent design without cracks or molding defects. They carefully considered.
  • the yield ratio is the ratio of the yield stress to the tensile strength, and the lower the yield ratio, the wider the range of load for obtaining a uniform elongation region, and the easier the plastic working.
  • the thickness distribution of the steel sheet at the time of forming becomes large, promoting reduction in thickness, and cracks tend to occur starting from inclusions present therein. Therefore, the present inventors investigated the relationship between the type and content of each element contained in the ferritic stainless steel and formability in order to impart formability to the extent that cylindrical deep drawing is possible.
  • Cylindrical deep drawing is a very difficult forming method, and it is effective in improving the formability to suppress the reduction in plate thickness at stress concentrated areas. If the plate thickness is reduced, the workability is lowered along with work hardening.
  • a detailed observation of the fracture surface of the molded product in which cracks occurred during the molding process confirmed a large number of Al oxides and TiN. Considering that these Al oxides and TiN promote cracking, the inventors have investigated steel components that can suppress the uneven distribution of Al oxides and the growth of TiN. Then, the inventors found that by applying a steel plate having a specific steel composition to a blank for deep drawing, forming that satisfies dimensional accuracy becomes possible.
  • a ferritic stainless steel sheet that is an embodiment of the present invention will be described below.
  • the ferritic stainless steel sheet of the present embodiment has C: 0.0200% or less, Si: 0.70% or less, Mn: 1.00% or less, P: 0.030% or less, S: 0.030% or less, in terms of % by mass. 005% or less, Cr: 11.0-19.5%, N: 0.020% or less, Al: 0.005-0.100%, O: 0.0050% or less, Ti: 0.03-0.
  • the symbols of the elements in the formulas (1) and (2) are the content (% by mass) of each element in the ferritic stainless steel sheet.
  • the ferritic stainless steel plate contains, by mass %, Mo: 0.05 to 0.50%, Ni: 0.05 to 0.50%, Cu: 0.01 to 1.0%, instead of part of Fe. 00% of 1 or 2 or more may be contained. Further, the ferritic stainless steel plate contains B: 0.0003 to 0.0050%, Ga: 0.0001 to 0.2%, W: 0.001 to 0.2%, in mass %, instead of part of Fe. 300% of one or more may be contained.
  • % which is a unit of component content, means % by mass.
  • C 0.0200% or less C deteriorates moldability and corrosion resistance, so the lower the content, the better, and the upper limit is made 0.0200% or less.
  • a preferable amount of C is 0.0030 to 0.0070%.
  • Si 0.70% or less Si may be contained as a deoxidizing element, but since it is a solid-solution strengthening element, the content should be small from the viewpoint of yield stress reduction, and the upper limit is 0.70%. 70% or less. However, since an excessive reduction in the amount of Si leads to an increase in refining costs, it is desirable to set the lower limit to 0.01% or more.
  • a preferable Si content is 0.05 to 0.50%.
  • Mn 1.00% or less Since Mn is a solid-solution strengthening element like Si, its content should be small from the viewpoint of yield stress reduction, and the upper limit is made 1.00% or less. However, since an excessive reduction in the amount of Mn leads to an increase in refining costs, it is desirable to set the lower limit to 0.01% or more. A preferred Mn content is 0.05 to 0.50%.
  • P 0.030% or less
  • P is an element that is unavoidably mixed from raw materials, and is a solid-solution strengthening element like Si and Mn. is 0.030% or less. It is preferably less than 0.030%, more preferably 0.025% or less. However, excessive reduction in the amount of P leads to an increase in refining costs, so the lower limit may be 0.010% or more.
  • S forms Ti 4 C 2 S 2 together with Ti and C in the case of Ti-added steel, and has the effect of fixing C. Since Ti 4 C 2 S 2 is a coarse precipitate that precipitates at high temperature, it has little effect on recrystallization and grain growth behavior, but if a large amount of this precipitate precipitates, it becomes a starting point for rust generation and deteriorates corrosion resistance. . Therefore, the upper limit of S is made 0.005% or less. However, since an excessive reduction in the amount of S leads to an increase in refining costs, the lower limit of the amount of S may be 0.0001% or more.
  • Cr 11.0-19.5% Cr needs to be contained in an amount of 11.0% or more to improve corrosion resistance, but an excessive content degrades toughness, degrades manufacturability, and increases yield stress. Therefore, the upper limit of Cr is set to 19.5% or less. A preferable Cr content is 13.0 to 17.5%.
  • N 0.020% or less N, like C, deteriorates formability and corrosion resistance, so the content should be as small as possible, and the upper limit is made 0.020% or less.
  • the lower limit may be set to 0.003% or more from the viewpoint of manufacturing cost for reduction.
  • a preferable amount of N is 0.005 to 0.015%.
  • Al 0.005-0.100% 0.005% or more of Al may be contained as a deoxidizing element.
  • an excessive Al content lowers formability and weldability, and may lead to deterioration of surface quality, so the upper limit is made 0.100% or less.
  • a preferable Al content is 0.010 to 0.080%.
  • O 0.0050% or less O lowers corrosion resistance and workability. Therefore, the amount of O must be kept low, and the upper limit is made 0.0050% or less. However, excessively reducing the O content increases the refining cost, so the lower limit of the O content may be 0.0001% or more. A preferable range of O content is 0.0005 to 0.0030%.
  • Ti 0.03-0.20% Ti combines with C, N, and S to form inclusions and has the effect of improving corrosion resistance, intergranular corrosion resistance, and deep drawability, so 0.03% or more is contained.
  • Ti is a solid-solution strengthening element, an excessive Ti content leads to an increase in solid-solution Ti, leading to a decrease in elongation, which is an index of stretchability. Therefore, the upper limit of Ti is set to 0.20% or less.
  • a preferable Ti amount is 0.08 to 0.12%.
  • Nb 0.010-0.300%
  • Nb is an element that improves formability and corrosion resistance, and the effect is exhibited by containing 0.010% or more. However, an excessive content causes a decrease in ductility due to solid solution strengthening, so the content is made 0.300% or less.
  • a preferable Nb content is 0.100 to 0.200%.
  • Sn 0.001-0.300% Containing Sn has the effect of lowering the yield ratio and improving the stretch workability. In order to obtain this effect, 0.001% or more of Sn is contained. On the other hand, if the content is excessive, the manufacturability deteriorates, so the upper limit is made 0.300% or less. A preferred Sn content is 0.020 to 0.200%.
  • Zr 0.001-0.080% 0.001% or more of Zr is contained as a deoxidizing element.
  • an excessive Zr content deteriorates formability, weldability and surface quality, so the upper limit is made 0.080% or less.
  • a preferable Zr content is 0.002 to 0.020%.
  • a passivation film exists in stainless steel, but phenomena such as oxides generated in the manufacturing process and concentration in the surface layer occur, and a wide variety of element concentration distributions exist.
  • Cr is an essential element for the formation of a passive film, but molds and mold coatings often contain Cr. Depending on the combination, mold galling may be induced due to affinity. Therefore, by allowing Al, which is a strong oxide, to exist in this passive film, it is possible to suppress die galling and ensure stable formability. Also, Sn is likely to exist on the surface and is softer than other elements, so it exerts an effect of relieving stress concentration.
  • the ferritic stainless steel sheet according to this embodiment preferably satisfies 0.6 ⁇ Cr+15 ⁇ Sn+8 ⁇ Al ⁇ 10.0.
  • Mo 0.05 to 0.50%
  • Ni 0.05 to 0.50%
  • Cu 0 .01 to 1.00% of one or two or more may be contained.
  • Mo, Ni, and Cu are elements that improve corrosion resistance, and in applications where corrosion resistance is required, one or more may be contained as necessary. Corrosion resistance is improved by containing 0.05% or more of each of Mo and Ni. Excessive contents of Mo and Ni cause hardening and deterioration of formability, so the upper limit of each of them is made 0.50% or less. Preferred Mo and Ni amounts are 0.10 to 0.30%, respectively. In addition, the effect of Cu is exhibited when the Cu content is 0.01% or more, but excessive Cu content deteriorates formability, particularly ductility, so the upper limit of the Cu content is made 1.00% or less. A preferable amount of Cu is 0.30 to 0.80%.
  • B 0.0003 to 0.0050%
  • Ga 0.0001 to 0.2%
  • W 0, instead of part of Fe .001 to 0.300% of one or two or more may be contained.
  • B is an element that improves secondary workability, and 0.0003% or more of B may be contained as necessary. However, since an excessive B content causes a decrease in elongation, the upper limit of the B content is 0.0050% or less. A preferable amount of B is 0.0010 to 0.0020%.
  • Ga is an element that forms GaS and improves corrosion resistance. By suppressing the precipitation of MnS, it is possible to eliminate the starting point of rust, so it is a very effective element. If the Ga content is less than 0.0001%, the effect is not recognized. On the other hand, an excessive content of Ga causes solid solution hardening. Therefore, the upper limit of the amount of Ga is 0.2% or less.
  • W like Nb and Ti, is an element that fixes C and N to prevent sensitization by Cr carbonitrides and improves corrosion resistance. In order to develop such an effect, the W content should be 0.001% or more. On the other hand, when the amount of W exceeds 0.300%, the stainless steel sheet is hardened and the workability is lowered. Therefore, the W content is preferably 0.300% or less.
  • the ferritic stainless steel sheet according to the present embodiment is composed of Fe and impurities (impurities include unavoidable impurities) other than the elements described above.
  • impurities include unavoidable impurities
  • it can be contained within a range that does not impair the effects of the present invention.
  • Bi, Pb, Se, H, etc. may be contained, but in that case, it is preferable to reduce them as much as possible.
  • the content ratio of these elements is controlled as long as the problems of the present invention are solved. % or less, and H may contain 0.01% or less.
  • a ferritic stainless steel plate having a thickness of 1.0 mm or less is formed.
  • a preferable plate thickness is 0.4 to 0.8 mm. Since the ferritic stainless steel sheet according to the present embodiment has excellent overhanging property due to the adjustment of the chemical composition, it is suitable for applications that require forming with a thin plate thickness, such as home appliances and kitchen equipment. It is particularly suitable for use.
  • Critical drawing ratio in cylindrical deep drawing 2.30 or more
  • Ferritic stainless steel has a high r-value suitable for drawing, but on the other hand, it has low breaking strength, and if the flow from the flange is delayed, cracks will occur on the side wall.
  • High lubrication conditions are applied to promote the inflow of material from the flange, but when the blank diameter is large, the contact length at the flange becomes long, so lubrication is likely to run out at the end of processing.
  • the range of components in which the effect can be obtained even when the lubrication is cut off in the final stage of processing is limited, and the critical drawing ratio at which the effect becomes clear is 2.30 or more.
  • the critical drawing ratio in cylindrical deep drawing is measured by the following procedure. Circular blanks with a plate thickness of 0.8 mm and various diameters are prepared, and each blank is subjected to cylindrical deep drawing. , Use a mold of the shape. The wrinkle pressing pressure is 10 kN. Then, the maximum diameter Dmax of the blank that can be formed without breaking is determined, and the ratio of Dmax to the punch diameter d (Dmax/d) is defined as the critical drawing ratio.
  • the ferritic stainless steel sheet according to the present embodiment has an average Lankford value (hereinafter referred to as an average r value, also referred to as an average plastic strain ratio) of 1.8 or more, and an in-plane anisotropy of the Lankford value ( ⁇ r) is preferably 0.5 or more, or more than 0.7.
  • the in-plane anisotropy ( ⁇ r) is set to 0.5 or more, the in-plane anisotropy in the deformation of the flange during molding becomes large, and the difference in the plate thickness of the flange causes the lubricant to be dissipated. Since there is a region to be secured, moldability can be further improved.
  • the average r value and ⁇ r can be measured by the plastic strain ratio test method of JIS Z 2254:2008.
  • the average r value can be obtained by the following formula (A) according to JIS Z 2254:2008.
  • the in-plane anisotropy ( ⁇ r) can be obtained by the following formula (B) according to JIS Z 2254:2008.
  • r0 indicates the r value in the rolling direction
  • r90 indicates the r value in the direction perpendicular to the rolling direction
  • r45 indicates the r value in the 45° rolling direction.
  • the ferritic stainless steel sheet of this embodiment can be produced by a general method, and is not particularly limited. That is, by casting a slab having the desired chemical composition by steelmaking and continuous casting, hot rolling, annealing and pickling after hot rolling, cold rolling, and final annealing after cold rolling are performed. do it.
  • the cold rolling rate is set to the range of 78 to 94%, and the final annealing after cold rolling
  • the temperature increase rate of is in the range of more than 20 ° C./sec, preferably 200 ° C./sec or less
  • the soaking rate and soaking time in the final annealing are respectively 830 to 950 ° C., and the range is 30 seconds to 2 minutes
  • the cooling rate from the end of soaking to 500° C. is preferably in the range of 15 to 30° C./sec.
  • the cold rolling rate is as shown in Table 2, the temperature rise rate in the final annealing after cold rolling is in the range of more than 20 ° C./sec, and the soaking rate and soaking in the final annealing The time was in the range of 830 to 950° C. and 30 seconds to 2 minutes, respectively, and the cooling rate from the end of soaking to 500° C. was in the range of 15 to 30° C./second. Using the steel sheets thus obtained, a cylindrical deep drawing test was performed.
  • an Eriksen 145-60 molding tester was used for the molding test.
  • a blank was obtained by cutting a steel plate into a disc shape.
  • the size of the blank was ⁇ 84 to 94 mm, and a mold with a shape of Die: inner diameter of 43 mm, Die: 4 mm, Punch: diameter of 40 mm was used.
  • the wrinkle pressing pressure was 10 kN.
  • Johnson wax #122 was lightly applied as a lubricant to the molding surface.
  • a molding test was conducted with the molding conditions fixed and the molding speed of the punch relative to the die set at 20 mm/min. It should be noted that the possibility of forming was determined by the presence or absence of cracks as draw forming without leaving a flange.
  • the 0.2% yield strength and elongation of the steel plate were measured using JIS No. 13B test pieces, in accordance with the conditions described in JIS Z 2241, and taken from the 0° direction parallel to the rolling direction. Further, the average r value and ⁇ r were measured under the condition that 16% strain was applied to the samples taken from the directions of 0°, 45° and 90° with respect to the rolling direction.
  • the critical drawing ratio in cylindrical deep drawing was measured by the following procedure. Circular blanks having a plate thickness of 0.8 mm and various diameters were prepared, and each blank was subjected to cylindrical deep drawing. A mold with a shape of 40 mm was used. The wrinkle pressing pressure was 10 kN. Then, the maximum diameter Dmax of the blank that can be formed without breaking was determined, and the ratio of Dmax to the diameter d of the punch (Dmax/d) was defined as the critical drawing ratio.
  • the present invention has industrial applicability in that it can provide a ferritic stainless steel sheet with excellent formability.
  • the ferritic stainless steel sheet according to the present invention can be used as a blank when manufacturing a thin-walled molded product that is required as a part for weight reduction of home electric appliances and kitchen equipment. , good moldability can be exhibited, so that it is possible to obtain a molded product that satisfies dimensional accuracy and design, and thus has industrial applicability.

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  • 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)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

Dans le but de fournir une feuille d'acier inoxydable ferritique présentant une excellente aptitude au formage, la présente invention concerne un procédé de formage pour un emboutissage en coupelles carrées d'une feuille d'acier inoxydable ferritique à une profondeur de formage cible, au moyen d'un formage à la presse à l'aide d'un poinçon et d'une matrice : la feuille d'acier inoxydable ferritique a une composition de composant qui contient C, Si, Mn, P, S, Cr, N, Al, O, Ti, Nb, Sn et Zr, tout en satisfaisant la formule (1) et la formule (2) ; la feuille d'acier inoxydable ferritique présente une épaisseur de feuille de 1,0 mm ou moins ; et la feuille d'acier inoxydable ferritique a un rapport d'étirage limite dans un emboutissage profond cylindrique de 2,30 ou plus.　(1) : (0,4 × Al + 0,5 × Zr + 0,1 × Ti)/O ≥ 12,0 (2) : 0,6 × Cr + 15 × Sn + 8 × Al ≥ 10,0
PCT/JP2021/042235 2021-11-17 2021-11-17 Feuille d'acier inoxydable ferritique WO2023089693A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
KR1020247015162A KR20240073121A (ko) 2021-11-17 2021-11-17 페라이트계 스테인리스 강판
PCT/JP2021/042235 WO2023089693A1 (fr) 2021-11-17 2021-11-17 Feuille d'acier inoxydable ferritique

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Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS57198248A (en) 1981-05-28 1982-12-04 Kawasaki Steel Corp Ferrite stainless steel with superior press formability
JPS5861258A (ja) 1981-10-08 1983-04-12 Nisshin Steel Co Ltd 張り出し性および二次加工性に優れたフエライト系ステンレス鋼
JP2004217996A (ja) 2003-01-14 2004-08-05 Nippon Steel Corp 成形性に優れたフェライト系ステンレス鋼板及びその製造方法
WO2014069543A1 (fr) * 2012-10-30 2014-05-08 新日鐵住金ステンレス株式会社 Feuille d'acier inoxydable ferritique avec une excellente résistance à la chaleur
WO2015113937A1 (fr) * 2014-01-28 2015-08-06 Tata Steel Ijmuiden B.V. Procédé permettant de produire une brame, une bande ou une feuille d'acier à teneur en carbone extrafaible ou à teneur en carbone ultrafaible, et brame, bande ou feuille produites au moyen de ce dernier
JP6050701B2 (ja) 2012-03-01 2016-12-21 新日鐵住金ステンレス株式会社 外装パネル用フェライト系ステンレス鋼板
JP2019173042A (ja) * 2018-03-26 2019-10-10 日鉄ステンレス株式会社 耐熱性に優れたフェライト系ステンレス鋼板および排気部品とその製造方法
WO2021100687A1 (fr) * 2019-11-19 2021-05-27 日鉄ステンレス株式会社 Tôle d'acier inoxydable ferritique

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6050701U (ja) 1983-09-12 1985-04-10 三洋電機株式会社 温風送風機付石油燃焼装置

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS57198248A (en) 1981-05-28 1982-12-04 Kawasaki Steel Corp Ferrite stainless steel with superior press formability
JPS5861258A (ja) 1981-10-08 1983-04-12 Nisshin Steel Co Ltd 張り出し性および二次加工性に優れたフエライト系ステンレス鋼
JP2004217996A (ja) 2003-01-14 2004-08-05 Nippon Steel Corp 成形性に優れたフェライト系ステンレス鋼板及びその製造方法
JP6050701B2 (ja) 2012-03-01 2016-12-21 新日鐵住金ステンレス株式会社 外装パネル用フェライト系ステンレス鋼板
WO2014069543A1 (fr) * 2012-10-30 2014-05-08 新日鐵住金ステンレス株式会社 Feuille d'acier inoxydable ferritique avec une excellente résistance à la chaleur
WO2015113937A1 (fr) * 2014-01-28 2015-08-06 Tata Steel Ijmuiden B.V. Procédé permettant de produire une brame, une bande ou une feuille d'acier à teneur en carbone extrafaible ou à teneur en carbone ultrafaible, et brame, bande ou feuille produites au moyen de ce dernier
JP2019173042A (ja) * 2018-03-26 2019-10-10 日鉄ステンレス株式会社 耐熱性に優れたフェライト系ステンレス鋼板および排気部品とその製造方法
WO2021100687A1 (fr) * 2019-11-19 2021-05-27 日鉄ステンレス株式会社 Tôle d'acier inoxydable ferritique

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