WO2014157578A1 - 研磨後の表面耐食性に優れるフェライト系ステンレス鋼及びその製造方法 - Google Patents

研磨後の表面耐食性に優れるフェライト系ステンレス鋼及びその製造方法 Download PDF

Info

Publication number
WO2014157578A1
WO2014157578A1 PCT/JP2014/059017 JP2014059017W WO2014157578A1 WO 2014157578 A1 WO2014157578 A1 WO 2014157578A1 JP 2014059017 W JP2014059017 W JP 2014059017W WO 2014157578 A1 WO2014157578 A1 WO 2014157578A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
polishing
corrosion resistance
stainless steel
ferritic stainless
Prior art date
Application number
PCT/JP2014/059017
Other languages
English (en)
French (fr)
Japanese (ja)
Inventor
佑一 田村
透 松橋
石丸　詠一朗
Original Assignee
新日鐵住金ステンレス株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 新日鐵住金ステンレス株式会社 filed Critical 新日鐵住金ステンレス株式会社
Priority to JP2015508733A priority Critical patent/JP5837258B2/ja
Priority to KR1020157023090A priority patent/KR101663207B1/ko
Priority to CN201480018150.3A priority patent/CN105074035B/zh
Publication of WO2014157578A1 publication Critical patent/WO2014157578A1/ja

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • C22C38/46—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

Definitions

  • the present invention relates to a ferritic stainless steel having excellent surface corrosion resistance after polishing and a method for producing the same.
  • Stainless steel is superior in corrosion resistance compared to ordinary steel, etc., so it may be used with the surface of the base exposed without the use of rust-proof coating for the purpose of effectively using metallic luster as a design.
  • Many in products such as kitchen appliances, home appliances, electronic devices, and appliances that are easily accessible to the public, such as elevators, refrigerators, kitchen sinks, and tableware, unevenness in a certain roughness range is obtained by polishing.
  • the anti-glare property and the anti-fingerprint stain resistance are improved by providing a streak pattern having, for example, polished eyes, and the metallic luster of the surface is secured.
  • a polishing belt with abrasive grains fixed with an adhesive on the stainless steel plate production line is pressed against the steel plate, or processed with a sponge that is mixed with resin and hardened after product shipment.
  • a method of rubbing a stainless steel product can be exemplified. Or the method of rotating the wheel (flap wheel) which bundled the thing which bundled the abrasive paper which fixed the abrasive grain with the adhesive agent in a ring shape, and pressed on stainless steel etc. is mentioned.
  • JIS G 4305 established by the Japanese Industrial Standards, No. 3, no.
  • the symbols such as 4, # 240, # 320, # 400, and HL define that a predetermined surface roughness can be designated.
  • Patent Document 1 when polishing with a polishing belt, a polishing oil is used for the purpose of improving cooling and grindability.
  • Patent Document 1 the formation of oxides is suppressed by adding an antioxidant to the polishing oil itself at the time of temperature rise due to frictional heat, an agent for preventing oil film breakage, and an agent for improving grindability, thereby preventing corrosion. Is preventing the decline.
  • Patent Document 2 discloses polishing corresponding to # 400 abrasive grains defined by JIS R 6001 such that the arithmetic average roughness Ra, which is the roughness of the surface, is in the range of 0.23 to 0.31 ⁇ m.
  • Patent Document 3 discloses that in stainless steel to which Mo is added, a halogen-containing acid treatment is performed for the purpose of removing the oxide film caused by the dense Mo formed on the surface in the annealing process and improving the polishability. Is doing. However, at this time, since the dissolution is non-uniform and grain boundary erosion also occurs, the Cr addition amount is increased, Cu, Ni is added, and the SiO 2 oxide film is left, so that the polishing property is excellent. In addition, a method for producing a stainless steel plate having excellent corrosion resistance is described.
  • Patent Document 4 discloses that after polishing a ferritic stainless steel sheet, the temperature is 1000 ° C. or higher and the time for which the temperature is maintained is 10 seconds or longer in a hydrogen gas atmosphere having a dew point of ⁇ 40 ° C. or lower, that is, a so-called BA atmosphere.
  • a manufacturing method is described in which the oxide in the oxide film produced by polishing is reduced by continuously heat-treating.
  • Ferritic stainless steel is liable to cause a decrease in surface corrosion resistance due to polishing burn due to heat generated during polishing. That is, in order to create design properties, when a polishing eye is provided, an oxide containing a large amount of Fe is formed on the polished surface by heat generated by friction between these abrasive grains and the stainless steel substrate.
  • the to oxides Cl such as Fe - when an aqueous solution containing adheres, hydroxides such as after dissolving the oxide solution such as Fe, etc. and oxygen chemically reacts with atmospheric Fe (OH) 2 To form a precipitate. As a result, red rust is generated on the stainless steel surface, resulting in an appearance in which the corrosion resistance of the substrate is lowered.
  • Patent Document 2 defines Ra and color tone of the surface, but many products are provided with relatively rough polishing marks such that Ra is 0.45 to 5.0 ⁇ m. In this case as well, red rust on the surface caused by adhesion of an aqueous solution containing Cl ⁇ cannot be suppressed.
  • the oxide film formed at the time of annealing is intentionally left on the surface of the steel sheet, thereby minimizing the dissolution of the base iron, especially the erosion at the grain boundary, and ensuring the corrosion resistance after polishing. is doing.
  • a relatively rough polishing grain is provided, even if the pickling process after annealing is devised to leave an oxide film during annealing, all the oxide film is removed during polishing. Therefore, since the Fe compound adhering to the surface of the ground iron corrodes, generation of red rust on the surface cannot be suppressed.
  • Aqueous solution containing - object of the present invention even when subjected to coarser grinding, Cl - red rust suppress ferritic stainless steel on the surface due to the deposition of an aqueous solution containing, and Cl after polishing with fewer steps It is an object to provide a method for producing a ferritic stainless steel having excellent surface corrosion resistance that can suppress red rust on the surface due to adhesion of steel.
  • the inventors have developed the oxide structure formed on the surface after polishing and the oxidation in salt water. We intensively investigated the corrosion resistance of the structure. As a result, it was found that the amount of grinding at the time of polishing can be suppressed and heat generation can be suppressed by adding a small amount of Si and surface hardening of stainless steel by applying a manufacturing method that increases the rolling reduction of temper rolling. In addition, combined with the addition of a small amount of Si and the suppression of heat generation during polishing, it is possible to form an oxide containing a large amount of SiO 2 on the surface, which causes red rust in salt water.
  • the present invention is as follows. (1) By mass%, C: 0.030% or less, N: 0.030% or less, Si: 0.15-3.0%, Mn: 1.5% or less, P: 0.04% or less, S: 0.01% or less, Cr: 12-22.5%, Nb: 0.60% or less, Ti: 0.60% or less, Al: 0.80% or less, the balance being Fe and inevitable A ferritic stainless steel excellent in surface corrosion resistance after polishing, which is an impurity and has a surface hardness Hv of 175 or more.
  • the average mass concentration of the elements excluding C, O and N contains Si of 5% or more and Fe of 75% or less, and the surface brightness L * value is 70 or more.
  • Ferritic stainless steel with excellent surface corrosion resistance after polishing characterized by (3) By mass%, C: 0.030% or less, N: 0.030% or less, Si: 0.15-3.0%, Mn: 1.5% or less, P: 0.04% or less, S: 0.01% or less, Cr: 12-22.5%, Nb: 0.60% or less, Ti: 0.60% or less, Al: 0.80% or less, the balance being Fe and inevitable It is made of impurities and has a polished surface with an arithmetic average roughness Ra of 0.45 to 5.0 ⁇ m.
  • the element concentration of the surface is measured by glow discharge optical emission spectrometry (GD-OES)
  • GD-OES glow discharge optical emission spectrometry
  • the average mass concentration of the elements excluding C, O and N contains Si of 5% or more and Fe of 75% or less, and the surface brightness L * value is 70 or more.
  • Si contains 5% or more and Fe contains 75% or less at an average mass concentration of the elements excluding C, O and N, and the surface brightness L * value is 70 Ferritic stainless steel with excellent surface corrosion resistance after polishing, characterized by taking the above values.
  • the ferritic stainless steel according to the present invention has good surface corrosion resistance in indoor applications that come into contact with chlorine-containing tap water, and the occurrence of red rust is suppressed even after polishing, and the surface aesthetics are improved. Maintained.
  • ferritic stainless steel of the present invention After forming the ferritic stainless steel of the present invention into a predetermined shape according to the purpose, by polishing as described in the present invention, among products such as kitchen appliances, home appliances, electronic devices, and instruments It can be suitably used as a part for exterior and daily necessities that are easy to touch.
  • C 0.030% or less C has an effect of improving strength by suppressing coarsening of grains by combination with hardening or a stabilizing element, but reduces intergranular corrosion resistance and workability of a welded portion.
  • the content In high-purity ferritic stainless steel, the content must be reduced, so the upper limit was made 0.030%. To reduce excessively deteriorates the refining cost, more desirably, the lower limit is made 0.002% and the upper limit is made 0.020%.
  • N 0.030% or less N, like C, reduces intergranular corrosion resistance and workability, so its content must be reduced, so its upper limit was made 0.030%. However, reducing excessively deteriorates the refining cost. More desirably, the lower limit is 0.002% and the upper limit is 0.020%.
  • Mn 1.5% or less Mn is an element that may not be contained in the present invention, but is also an element useful as a deoxidizing element. However, if Mn is added excessively, MnS that becomes a starting point of corrosion tends to be generated, so the upper limit was made 1.5%. Since it is used as a deoxidizing element, 0.01% or more is preferable.
  • the lower limit of the content is preferably 0.01% and the upper limit is preferably 0.60%. More desirably, the lower limit is 0.05% and the upper limit is 0.3%.
  • P 0.04% or less P not only lowers weldability and workability, but also tends to cause intergranular corrosion, so P needs to be kept low. Therefore, the content is set to 0.04% or less. More preferably, the lower limit is 0.001% and the upper limit is 0.03%.
  • S 0.01% or less S needs to be reduced because water-soluble inclusions such as the above-mentioned CaS and MnS, which are the starting points of corrosion, are generated. Therefore, the content is made 0.01% or less. However, excessive reduction leads to cost deterioration. More preferably, the lower limit is 0.0001% and the upper limit is 0.006%.
  • Cr 12-22.5% Cr is the most important element for securing the corrosion resistance of stainless steel, and at least 12% is necessary because it stabilizes the ferrite structure. Cr is concentrated in the oxide film on the surface in the same manner as Si described later, and the generation of red rust after polishing is suppressed by relatively suppressing the concentration of Fe. Increasing Cr improves the corrosion resistance after polishing, but lowers workability and manufacturability, so the upper limit was made 22.5%. Preferably, the lower limit is 13.5% and the upper limit is 21.0%, more preferably the lower limit is 16.0% and the upper limit is 20.0%. More preferably, the lower limit is 16.5% and the upper limit is 18.0%.
  • Si 0.15-3.0%
  • Si is an extremely important element in the present invention, is generally effective in corrosion resistance and oxidation resistance, and is an element added as a deoxidizer.
  • the concentration of Fe oxide is relatively suppressed. Therefore, the occurrence of red rust after polishing is suppressed.
  • the upper limit was made 3.0%. Desirably, the upper limit is less than 2.5%. More desirably, it is 1.5% or less. More desirably, it is 1.0% or less.
  • the lower limit is desirably 0.3% or more, and more desirably 0.4% or more.
  • Al 0.80% or less
  • Al is an element that does not need to be contained, but is useful as a deoxidizing element like Si, and also has the effect of controlling the composition of non-metallic inclusions and refining the structure. .
  • the upper limit is set to 0.80%.
  • the lower limit value does not need to be set in particular.
  • the lower limit value may be 0.01% or more from an economic viewpoint. Desirably, the lower limit is 0.01% and the upper limit is 0.80%. More desirably, the lower limit is 0.03%, and the upper limit is 0.5%.
  • Ti 0.60% or less Ti is an important element that generally suppresses intergranular corrosion and improves workability by fixing C and N in a weld zone of ferritic stainless steel. However, excessive addition causes surface flaws during production, so the range was made 0.60% or less.
  • the lower limit may be 0.03% or more. 0.05% or more is desirable, and more desirably 0.08% or more. Desirably, the lower limit is 0.08 and the upper limit is 0.30%. More desirably, the lower limit is 0.08% and the upper limit is 0.20%.
  • Nb 0.60% or less
  • Nb is an extremely important element for fixing C and N like Ti, suppressing intergranular corrosion of the welded portion, and improving workability. Moreover, when it precipitates as a carbide
  • the lower limit value may be set to 0.03% or more.
  • the lower limit is preferably 0.05%, more preferably 0.08%.
  • a desirable range is to set the lower limit to 0.10% and the upper limit to 0.30%. A more desirable range is to set the lower limit to 0.10% and the upper limit to 0.20%. In addition, as long as one of Ti and Nb is contained, the other may not be contained.
  • Sn 0.005 to 1.0% Since Sn hardens the metal structure like Si, it can reduce the amount of grinding during polishing, and as a result, is an important element that suppresses polishing heat and suppresses oxide formation. At the same time, it is an important element for suppressing the corrosion rate and improving the flow rust resistance after polishing. Since the effect is manifested at 0.005% or more, the lower limit is set to 0.005%. 0.05% or more is desirable, and further 0.08% or more is desirable. Excessive addition deteriorates manufacturability and cost, so the upper limit was made 1.0%, preferably 0.5%. A more desirable upper limit of Sn is 0.4%. Therefore, the Sn range is to set the lower limit to 0.005% and the upper limit to 1.0%. Desirably, the lower limit is 0.05% and the upper limit is 0.5%. More desirably, the lower limit is 0.08% and the upper limit is 0.4%.
  • Cu 1.5% or less
  • Cu is not essential, but may be contained in an amount of 0.01% or more as an inevitable impurity when scrap is used as a raw material.
  • Cu suppresses the corrosion rate, and is added as necessary to improve the flow rust resistance after polishing in the same manner as Sn. It is good to add 0.05% or more. Desirably, it is 0.09% or more, and more desirably 0.15% or more. However, excessive addition deteriorates manufacturability and cost, so the upper limit was made 1.5%.
  • a desirable upper limit is 1.0%.
  • Ni 0.50% or less
  • Ni is not essential, but if contained, it suppresses the active dissolution rate and is very effective for passivation. However, excessive addition reduces workability and not only destabilizes the ferrite structure but also deteriorates the cost, so it was made 0.50% or less. Desirably, it was made into less than 0.35%. The lower limit is preferably 0.05%. Therefore, the desirable range of Ni is 0.05% or more and less than 0.35%.
  • Mo 3.0% or less Mo is effective in repairing the passive film, and is an element that is very effective for improving the corrosion resistance.
  • Mo is effective in improving the pitting corrosion resistance in combination with Cr.
  • the upper limit is made 3.0%. More desirably, the lower limit is 0.30% and the upper limit is 2.00%.
  • B 0.003% or less
  • B is a grain boundary strengthening element effective for improving secondary work brittleness, and can be added as necessary.
  • the lower limit is made 0.0001%.
  • the upper limit is 0.003%. More desirably, the lower limit is 0.0002% and the upper limit is 0.0020%.
  • V 1.0% or less V improves the weather resistance and crevice corrosion resistance, and can suppress the use of Cr and Mo and add V to ensure excellent workability. Can be added.
  • the lower limit is preferably 0.03%. However, excessive addition of V reduces workability and also saturates the effect of improving corrosion resistance, so the upper limit is made 1.0%. More desirably, the lower limit is 0.05% and the upper limit is 0.50%.
  • Sb 0.001 to 0.3%
  • Sb is effective in improving the corrosion resistance, and may be added in an amount of 0.3% by mass or less as necessary.
  • the lower limit of the amount of Sb is set to 0.001% by mass.
  • the amount of Sb is 0.01% by mass or more from the viewpoint of manufacturability and cost.
  • the upper limit of the amount of Sb is preferably 0.1% by mass.
  • Ga 0.0002 to 0.1% Ga may be added in an amount of 0.1% by mass or less in order to improve corrosion resistance and suppress hydrogen embrittlement. From the viewpoint of the formation of sulfides and hydrides, the lower limit of Ga content is 0.0002% by mass. Furthermore, the amount of Ga is preferably 0.0020% by mass or more from the viewpoint of manufacturability and cost.
  • Ta 0.50% or less Ta is an element that improves high-temperature strength, and can be added as necessary. However, addition of an excessive amount of Ta causes a decrease in normal temperature ductility and a decrease in toughness, so 0.50% by mass is made the upper limit of the Ta amount. In order to achieve both high temperature strength and ductility / toughness, the Ta content is preferably 0.05% by mass or more and 0.5% by mass or less.
  • W 0.50% or less W is effective in improving the high-temperature strength, and is added at 0.01% or more as necessary. Further, if added over 0.50%, the solid solution strengthening is too large and the mechanical properties are lowered, so the lower limit is made 0.01% and the upper limit is made 0.50%. Considering the manufacturing cost and hot-rolled sheet toughness, it is desirable that the lower limit is 0.02% and the upper limit is 0.15%.
  • Co 0.50% or less Co is effective for improving wear resistance and high-temperature strength, and is added at 0.01% or more as necessary. Moreover, even if added over 0.50%, the effect is saturated, and mechanical properties are deteriorated due to solid solution strengthening. Therefore, the lower limit is set to 0.01% and the upper limit is set to 0.50%. Add in. From the viewpoint of manufacturing cost and stability of high temperature strength, it is desirable to add in a range where the lower limit is 0.05% and the upper limit is 0.20%.
  • Mg 0.01% or less Mg is an element effective for refining the solidified structure in the steel making process, and is added in an amount of 0.0003% or more as necessary. Further, even if added over 0.01%, the effect is saturated, and the corrosion resistance due to Mg sulfide or oxide is likely to be lowered. Therefore, the lower limit is set to 0.0003%, and the upper limit is set to 0.00. Add within the range of 01%. In consideration of the fact that the Mg addition in the steelmaking process causes oxidative combustion of Mg and the yield decreases and the cost increases greatly, the lower limit is preferably 0.0005% and the upper limit is preferably 0.0015%.
  • Ca 0.0030% or less Ca is an important desulfurization element in the steel making process, and also has a deoxygenating effect, so is added at 0.0003% or more as necessary. Moreover, even if added over 0.0030%, the effect is saturated, and the corrosion resistance is reduced due to Ca granulated material and the workability is deteriorated due to oxide. Therefore, the lower limit is made 0.0003%.
  • the upper limit is added within a range of 0.0030%. Considering manufacturability such as slag treatment, it is desirable that the lower limit is 0.0005% and the upper limit is 0.0015%.
  • Zr 0.30% or less Zr is added in an amount of 0.01% or more as necessary in order to form a carbonitride and suppress the formation of Cr carbonitride and improve the corrosion resistance like Nb and Ti. To do. Moreover, even if added over 0.30%, the effect is saturated and the formation of large oxides can cause surface defects. Therefore, the lower limit is set to 0.01% and the upper limit is set to 0.30%. Add within range. Since it is an expensive element compared with Ti and Nb, considering the manufacturing cost, it is desirable that the lower limit is 0.02% and the upper limit is 0.05%.
  • REM rare earth element: 0.20% or less REM is effective in improving oxidation resistance, and is added at 0.001% or more as necessary. Moreover, even if added over 0.20%, the effect is saturated, and the corrosion resistance is reduced by the REM granulated material. Therefore, the lower limit is set to 0.001% and the upper limit is added to 0.20%. To do. Considering the workability and manufacturing cost of the product, it is desirable that the lower limit is 0.002% and the upper limit is 0.05%.
  • REM rare earth element
  • Sc scandium
  • Y yttrium
  • 15 elements lanthanoid
  • La lanthanum
  • Lu lutetium
  • Hf, Bi, etc. may be added in an amount of 0.001 to 0.1% by mass as necessary. Note that the amount of generally harmful elements such as As and Pb and impurity elements is preferably reduced as much as possible.
  • the arithmetic average roughness Ra of the surface is not particularly limited, but it is desirable that the stainless steel plate has a polishing grain having Ra of 0.45 to 5.0 ⁇ m.
  • Ra is 0.45 ⁇ m or more, the method described in Patent Document 2 cannot prevent the corrosion resistance of the steel sheet surface from being lowered, and for the first time in the present invention, it is possible to prevent the corrosion resistance from being degraded by polishing the steel sheet surface.
  • the polished stainless steel plate of the present invention has a surface layer containing 5% or more of the Si concentration, so-called SiO 2 rich oxidation, even though the Si composition is 0.15 to 3.0% of the steel plate. It is characterized in that a surface layer of an object is formed.
  • the concentration of Si in the surface layer as described above occurs when the surface is oxidized by heat generation during polishing. Therefore, the lower limit of Ra of the present invention is set to 0.45 ⁇ m.
  • the upper limit of Ra is set to 5.0 ⁇ m.
  • the stainless steel plate of the present invention has an average ratio of elements excluding C, O and N at a depth of 10 nm from the surface when the element concentration on the surface is measured by glow discharge optical emission spectrometry (GD-OES).
  • GD-OES glow discharge optical emission spectrometry
  • Si contains 5% or more and Fe contains 75% or less. Since Si has a high oxygen affinity, it is preferentially oxidized at a high temperature. Therefore, by setting the element concentration on the surface within this range, it is possible to prevent the occurrence of red rust on the surface and prevent the surface aesthetics from being impaired.
  • the steel component of the present invention, particularly the Si content is within the scope of the present invention, and Ra is 0 only after temper rolling with a rolling reduction of 0.5% to 5.0% as described below. Even in the case of polishing having a polishing mesh of .45 ⁇ m or more, the elemental concentration of the surface can be 5% or more for Si and 75% or less for Fe.
  • the stainless steel plate of the present invention is characterized in that the surface brightness L * value is 70 or more. This is because when L * is less than 70, the Si concentration in the range from the surface to 10 nm is 5% or less.
  • the lightness L * value means the CIE lightness in the L * a * b * color system defined in JIS Z 8729.
  • the above-mentioned steel having the proper composition is melted by a known method, and is made into a slab by a known method such as continuous casting. After the slab is reheated to 1100 to 1200 ° C, the finishing temperature is 700 to 900 ° C. Perform hot rolling to obtain a hot-rolled steel strip. Subsequently, this hot-rolled steel strip is annealed at a temperature of 800 to 1100 ° C., pickled, and then cold-rolled to obtain a cold-rolled steel strip having a finished thickness of 6.0 mm or less. If necessary, the cold-rolled steel strip is annealed in a coke oven combustion gas atmosphere, for example, at about 950 ° C. for about 60 seconds, and then subjected to a salt treatment, followed by a dipping treatment in a nitric hydrofluoric acid solution, or Electrolytic treatment in neutral salt.
  • the surface of the cold-rolled steel strip is hardened by temper rolling at a rolling reduction of 0.5% to 5.0%. Rolling at a rolling reduction of more than 5.0% may lead to the capacity limit of the equipment and the occurrence of surface flaws, so it is necessary to take measures for equipment and surface flaws when applying.
  • temper rolling is performed only for the purpose of adjusting the brightness and roughness of the surface, and therefore it is premised that annealing is not performed, and therefore is operated only in a range where work hardening does not occur so much.
  • the rolling reduction is less than 0.5%.
  • temper rolling is performed at a rolling reduction larger than that of normal temper rolling, and in the present invention, the Si content is 0.15 at a rolling reduction of 0.5% or more. Combined with -3.0%, the effect of hardening the surface was recognized.
  • the rolling reduction of temper rolling is desirably 1% or more. In consideration of the facility capacity and surface defects, the upper limit is preferably 4%. This curing can suppress heat generation when the surface is polished.
  • the surface hardening by temper rolling in the present invention varies depending on the hardness (hereinafter referred to as Hv s value) and the reduction rate of the annealed cold-rolled steel strip before temper rolling.
  • Hv s value the hardness after temper rolling
  • the reduction rate of the annealed cold-rolled steel strip before temper rolling For example, when Hv s is 170, the hardness after temper rolling (hereinafter referred to as Hv value) when the rolling reduction is 0.5%, 1.0%, 4.0%, 5.0% Becomes 172, 174, 184, 188.
  • Hv value after temper rolling required to sufficiently obtain the corrosion resistance after polishing was 175 or more. It is desirably 180 or more, and more desirably 182 or more.
  • the upper limit of the surface hardness after the temper rolling is not particularly limited, but the upper limit of the Hv value is desirably 195 because the viewpoint of productivity and the effect are saturated.
  • the product plate of the stainless steel plate or the processed product is polished to have an arithmetic average roughness Ra of 0.45 to 5.0 ⁇ m.
  • the size of the abrasive grains adhering to the polishing belt used for polishing becomes finer by use. That is, when the same belt portion is continuously used and the abrasive grains adhering to the belt are worn or dropped, the size of the abrasive grains becomes finer than that in a new state. In general, this is called “blindness”, and the actual count or the particle size number of the polishing belt used increases.
  • the count of the polishing belt and the size of the abrasive grains may be finely changed depending on the usage state of the polishing belt so that the surface roughness at the time of finishing is arbitrary Ra within the range of 0.45 to 5.0 ⁇ m. .
  • Si was 5% or more and Fe was 75% or less at an average mass concentration of elements excluding C and O at a depth of 10 nm from the surface. Even if a relatively rough polishing is performed by setting the Si addition amount to 0.3 to 3.0% and performing the temper rolling as specified above to perform surface hardening so that the surface is included. By reducing the amount of grinding sometimes, temperature rise is suppressed, Si is preferentially oxidized, and formation of Fe oxide on the surface is further suppressed. Further, when the amount of grinding is reduced by surface hardening and preferential oxidation of Si occurs, the formation of Fe oxide is suppressed, and the surface brightness L * value takes a value of 70 or more.
  • the steels of the present invention having the composition shown in Table 2-1 were melted in a vacuum melting furnace and the comparative steels B1 to B19 shown in Table 2-2 were cast to obtain a 30 kg steel ingot, This steel ingot was heated to 1150 ° C. and hot-rolled in a temperature range of 1150 to 900 ° C. to obtain a hot rolled sheet having a thickness of 3 mm. Subsequently, these hot rolled sheets were annealed at 950 ° C., and then cold rolling and annealing were repeated to obtain cold rolled sheets having a sheet thickness of 1.0 mm.
  • the surface was polished with a polishing belt having an arbitrary abrasive grain size such that the arithmetic average roughness Ra was in the range of 0.45 to 5.0 ⁇ m.
  • Ra was measured in accordance with JIS B0601 at a measurement length of 5 mm, a measurement speed of 0.60 mm / s, and a cutoff wavelength of 0.8 mm. Table 3 shows Ra.
  • ⁇ GD-OES analysis> The sample was cut into a size of 30 mm ⁇ 30 mm, the sputtering diameter was 4 mm, and the sputtering interval was 2.5 msec.
  • each element was analyzed in the depth direction up to 100 nm using GDA-750HP manufactured by Spectrum Analytical GmbH.
  • the Si concentration was calculated by the mass ratio of elements excluding the light elements C, O, and N in the range from the surface to 10 nm.
  • ⁇ Corrosion resistance test> The corrosion resistance was evaluated by the salt spray test (SST) defined in JIS Z2371 using the sample after polishing.
  • the condition of the salt spray test was that a 5% by mass sodium chloride aqueous solution was continuously sprayed at a temperature of 35 ° C. for 96 hours.
  • Corrosion resistance is evaluated based on the degree of rust generation on the surface, and the evaluation results are shown in seven stages A to G. As for the corrosion resistance evaluation result, A is the best, G is the worst result, and stage C is set as the lower limit of acceptance.
  • the salt spray test a 5% sodium chloride aqueous solution was continuously sprayed at 35 ° C. for 96 hours. Specific evaluation criteria for corrosion resistance are shown in Table 1.
  • Table 3 shows the rolling reduction of temper rolling, the surface Ra, the L * value by brightness measurement, the mass concentration of Si and Fe in the thickness range of 10 nm from the surface, and the corrosion resistance evaluation results.
  • FIG. 1 shows the determination by the corrosion resistance evaluation value after the salt spray test in the relationship between the mass concentration (mass%) of Si contained in the thickness of 10 nm after polishing and the L * value measured with a color difference meter. A graph is shown.
  • Tables 2-1 and A1 to A34 in Table 3 are examples of the present invention. These invention examples contain components within the scope of the present invention, and have the surface arithmetic mean roughness Ra, surface Si, Fe concentration, surface brightness L * value specified in the present invention, and as a result, polishing Later, excellent surface corrosion resistance was achieved.
  • Tables 2-2 and B1 to B19 in Table 3 are comparative examples.
  • B1 and B19 have a small Si addition amount, the Si concentration on the surface is low, and SiO 2 cannot be sufficiently formed on the surface. Furthermore, since the hardness is small and the polishing amount is increased, heat generation is increased and oxidation is promoted. Therefore, it is inferior in the corrosion resistance evaluation. Since B2 and B4 have a large N addition amount, intergranular corrosion is likely to progress, and inferior in corrosion resistance evaluation. In particular, since the amount of Cr added is small in B2, the concentration of Fe in the oxide film cannot be sufficiently suppressed, and the corrosion resistance is significantly lower than that in B4.
  • B3 has a large amount of C added, intergranular corrosion is likely to proceed as in the case where the amount of N added is large, and inferior in corrosion resistance evaluation.
  • B5, like B2, has a small amount of Cr added, so it cannot sufficiently suppress the concentration of Fe in the oxide film, and the corrosion resistance is inferior.
  • B6 or B7 has a large amount of Mn or S added, it becomes easy to generate MnS as a starting point of corrosion, and the corrosion resistance is inferior.
  • B8 or B9 has a large amount of Al or Ti added, non-metallic inclusions are coarsened and surface flaws are observed, which is inappropriate for the present invention.
  • B10 or B11, B12, B13, B14, B15, B18 has a large amount of Cr or Nb, V, Cu, Sn, Ni, Si added, the workability and manufacturability are reduced, and the cost is further increased. It is inappropriate for the invention.
  • B17 contains P at P> 0.04%, the workability was lowered and the SST evaluation was also low.
  • B16 has a temper rolling reduction ratio of less than 0.5%, its surface hardness is insufficient and its corrosion resistance is inferior.
  • the ferritic stainless steel sheet of the present invention is suitable for use in exteriors and daily necessities that are easy to touch among products such as kitchen equipment, home appliances, electronic equipment, and equipment.

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)
PCT/JP2014/059017 2013-03-27 2014-03-27 研磨後の表面耐食性に優れるフェライト系ステンレス鋼及びその製造方法 WO2014157578A1 (ja)

Priority Applications (3)

Application Number Priority Date Filing Date Title
JP2015508733A JP5837258B2 (ja) 2013-03-27 2014-03-27 研磨後の表面耐食性に優れるフェライト系ステンレス鋼及びその製造方法
KR1020157023090A KR101663207B1 (ko) 2013-03-27 2014-03-27 연마 후의 표면 내식성이 우수한 페라이트계 스테인리스강 및 그 제조 방법
CN201480018150.3A CN105074035B (zh) 2013-03-27 2014-03-27 研磨后的表面耐蚀性优异的铁素体系不锈钢及其制造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2013066353 2013-03-27
JP2013-066353 2013-03-27

Publications (1)

Publication Number Publication Date
WO2014157578A1 true WO2014157578A1 (ja) 2014-10-02

Family

ID=51624534

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2014/059017 WO2014157578A1 (ja) 2013-03-27 2014-03-27 研磨後の表面耐食性に優れるフェライト系ステンレス鋼及びその製造方法

Country Status (4)

Country Link
JP (1) JP5837258B2 (ko)
KR (1) KR101663207B1 (ko)
CN (1) CN105074035B (ko)
WO (1) WO2014157578A1 (ko)

Cited By (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104451406A (zh) * 2014-11-18 2015-03-25 山东省源通机械股份有限公司 高耐盐碱腐蚀不锈钢铸件及其制备方法
JP2015145531A (ja) * 2014-02-04 2015-08-13 新日鐵住金ステンレス株式会社 研磨後の耐食性に優れたフェライト系ステンレス鋼
WO2018034044A1 (ja) * 2016-08-19 2018-02-22 日新製鋼株式会社 水道管内張りの金属パネル用ステンレス鋼板及びそのステンレス鋼板を用いた水道管の金属パネル内張り方法
JP6307188B1 (ja) * 2017-02-23 2018-04-04 日新製鋼株式会社 黒色フェライト系ステンレス鋼板
KR20180043827A (ko) * 2015-09-30 2018-04-30 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스 강판
EP3214198A4 (en) * 2014-10-31 2018-09-05 Nippon Steel & Sumikin Stainless Steel Corporation Ferrite-based stainless steel with high resistance to corrosiveness caused by exhaust gas and condensation and high brazing properties and method for manufacturing same
EP3278895A4 (en) * 2015-03-31 2018-09-05 Nippon Steel & Sumitomo Metal Corporation Steel sheet for hot stamping, method for manufacturing same, and hot stamp molded article
JP2018168415A (ja) * 2017-03-29 2018-11-01 新日鐵住金ステンレス株式会社 フェライト系ステンレス鋼
EP3438313A4 (en) * 2016-03-30 2019-08-21 Nippon Steel Nisshin Co., Ltd. NB-CONTAINING FERRITIC STAINLESS STEEL PLATE AND MANUFACTURING METHOD THEREFOR
WO2019189174A1 (ja) * 2018-03-27 2019-10-03 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびその製造方法、フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
JP2019173073A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
JP2019173075A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
JP2019173072A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびその製造方法、ならびに燃料電池用部材
JP2019173074A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
JP2020063499A (ja) * 2018-10-19 2020-04-23 日鉄ステンレス株式会社 ステンレス鋼
JP2020100866A (ja) * 2018-12-21 2020-07-02 日鉄ステンレス株式会社 耐水素脆性と耐低温脆性に優れたＣｒ系ステンレス鋼
US10752973B2 (en) 2014-10-31 2020-08-25 Nippon Steel & Sumikin Stainless Steel Corporation Ferrite-based stainless steel with high resistance to corrosiveness caused by exhaust gas and condensation and high brazing properties and method for manufacturing same
US11091824B2 (en) * 2014-07-22 2021-08-17 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel and method for producing same, and heat exchanger equipped with ferritic stainless steel as member

Families Citing this family (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106636909A (zh) * 2017-01-13 2017-05-10 南京理工大学 一种耐腐蚀软磁铁素体不锈钢
MX2019011210A (es) * 2017-03-29 2019-11-05 Nippon Steel Stainless Steel Corp Acero inoxidable ferritico que tiene resistencia al desgaste superior a alta temperatura, metodo de produccion para lamina de acero inoxidable ferritico, componentes de escape, componentes de deslizamiento de alta temperatura y componentes de turbocompresor.
KR102020514B1 (ko) * 2017-12-20 2019-09-10 주식회사 포스코 확관 가공성이 향상된 페라이트계 스테인리스강 및 그 제조방법
CN108456821B (zh) * 2017-12-25 2020-07-14 宁波骑士马具用品制造有限公司 一种马蹄钉用金属线材及其制备方法
CN108081705A (zh) * 2018-02-09 2018-05-29 河南工学院 一种耐腐蚀复合金属材料
KR102302386B1 (ko) * 2019-05-13 2021-09-15 주식회사 포스코 내식성이 향상된 페라이트계 스테인리스강
WO2020250784A1 (ja) * 2019-06-11 2020-12-17 三菱瓦斯化学株式会社 水性組成物、これを用いたステンレス鋼表面の粗化処理方法、ならびに粗化処理されたステンレス鋼およびその製造方法
CN110284075B (zh) * 2019-07-03 2020-10-27 衡阳市金则利特种合金股份有限公司 电磁阀动铁芯的生产工艺
CN110318004B (zh) * 2019-07-03 2020-10-20 衡阳市金则利特种合金股份有限公司 电磁阀用合金材料与静铁芯的生产工艺
EP4119697A4 (en) * 2020-03-12 2024-04-17 Nippon Steel Stainless Steel Corp FERRITIC STAINLESS STEEL AND ITS MANUFACTURING METHOD
WO2021241131A1 (ja) * 2020-05-28 2021-12-02 日鉄ステンレス株式会社 オーステナイト系ステンレス鋼材及び耐食性部材
CN114901848B (zh) * 2020-05-28 2023-09-19 日铁不锈钢株式会社 铁素体系不锈钢钢材及耐蚀性构件
KR20220107270A (ko) * 2020-05-28 2022-08-02 닛테츠 스테인레스 가부시키가이샤 페라이트·오스테나이트 2상계 스테인리스 강재 및 내식성 부재
KR20230094726A (ko) * 2021-12-21 2023-06-28 주식회사 포스코 내식성과 성형성이 향상된 배기계 강관용 강판 및 그 제조방법

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005307293A (ja) * 2004-04-22 2005-11-04 Nisshin Steel Co Ltd 耐指紋性，耐疵付き性，加工性に優れたフェライト系ステンレス鋼ｂａ仕上げ材及びその製造方法
JP2007239060A (ja) * 2006-03-10 2007-09-20 Nisshin Steel Co Ltd 表面硬化フェライト系ステンレス鋼板
JP2008266696A (ja) * 2007-04-18 2008-11-06 Jfe Steel Kk オーステナイト系ステンレス鋼板との溶接性に優れるフェライト系ステンレス鋼板およびその製造方法
JP2009041041A (ja) * 2007-08-06 2009-02-26 Jfe Steel Kk 水周り部材用フェライト系ステンレス鋼板
JP2012193392A (ja) * 2011-03-14 2012-10-11 Nippon Steel & Sumikin Stainless Steel Corp 耐銹性と防眩性に優れた高純度フェライト系ステンレス鋼板
JP2012214897A (ja) * 2011-03-31 2012-11-08 Nippon Steel & Sumikin Stainless Steel Corp 耐加工肌荒れ性に優れるフェライト系ステンレス鋼板

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4070253B2 (ja) * 1996-04-24 2008-04-02 新日鐵住金ステンレス株式会社 防眩性に優れた高耐銹フェライト系ステンレス鋼板およびその製造方法
JP2001269851A (ja) 2000-03-24 2001-10-02 Nisshin Steel Co Ltd ステンレス鋼帯の研磨方法
JP2004330394A (ja) 2003-05-12 2004-11-25 Nisshin Steel Co Ltd ステンレス鋼製品およびステンレス鋼の表面研磨方法
JP5018257B2 (ja) 2007-06-11 2012-09-05 Ｊｆｅスチール株式会社 研磨性および耐食性に優れるフェライト系ステンレス鋼板およびその製造方法
JP2010229488A (ja) 2009-03-27 2010-10-14 Nisshin Steel Co Ltd フェライト系ステンレス鋼研磨仕上げ材の製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005307293A (ja) * 2004-04-22 2005-11-04 Nisshin Steel Co Ltd 耐指紋性，耐疵付き性，加工性に優れたフェライト系ステンレス鋼ｂａ仕上げ材及びその製造方法
JP2007239060A (ja) * 2006-03-10 2007-09-20 Nisshin Steel Co Ltd 表面硬化フェライト系ステンレス鋼板
JP2008266696A (ja) * 2007-04-18 2008-11-06 Jfe Steel Kk オーステナイト系ステンレス鋼板との溶接性に優れるフェライト系ステンレス鋼板およびその製造方法
JP2009041041A (ja) * 2007-08-06 2009-02-26 Jfe Steel Kk 水周り部材用フェライト系ステンレス鋼板
JP2012193392A (ja) * 2011-03-14 2012-10-11 Nippon Steel & Sumikin Stainless Steel Corp 耐銹性と防眩性に優れた高純度フェライト系ステンレス鋼板
JP2012214897A (ja) * 2011-03-31 2012-11-08 Nippon Steel & Sumikin Stainless Steel Corp 耐加工肌荒れ性に優れるフェライト系ステンレス鋼板

Cited By (28)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2015145531A (ja) * 2014-02-04 2015-08-13 新日鐵住金ステンレス株式会社 研磨後の耐食性に優れたフェライト系ステンレス鋼
US11091824B2 (en) * 2014-07-22 2021-08-17 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel and method for producing same, and heat exchanger equipped with ferritic stainless steel as member
US10752973B2 (en) 2014-10-31 2020-08-25 Nippon Steel & Sumikin Stainless Steel Corporation Ferrite-based stainless steel with high resistance to corrosiveness caused by exhaust gas and condensation and high brazing properties and method for manufacturing same
EP3214198A4 (en) * 2014-10-31 2018-09-05 Nippon Steel & Sumikin Stainless Steel Corporation Ferrite-based stainless steel with high resistance to corrosiveness caused by exhaust gas and condensation and high brazing properties and method for manufacturing same
CN104451406A (zh) * 2014-11-18 2015-03-25 山东省源通机械股份有限公司 高耐盐碱腐蚀不锈钢铸件及其制备方法
EP3278895A4 (en) * 2015-03-31 2018-09-05 Nippon Steel & Sumitomo Metal Corporation Steel sheet for hot stamping, method for manufacturing same, and hot stamp molded article
KR20180043827A (ko) * 2015-09-30 2018-04-30 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스 강판
KR102067154B1 (ko) * 2015-09-30 2020-01-16 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스 강판
EP3438313A4 (en) * 2016-03-30 2019-08-21 Nippon Steel Nisshin Co., Ltd. NB-CONTAINING FERRITIC STAINLESS STEEL PLATE AND MANUFACTURING METHOD THEREFOR
WO2018034044A1 (ja) * 2016-08-19 2018-02-22 日新製鋼株式会社 水道管内張りの金属パネル用ステンレス鋼板及びそのステンレス鋼板を用いた水道管の金属パネル内張り方法
WO2018155075A1 (ja) * 2017-02-23 2018-08-30 日新製鋼株式会社 黒色フェライト系ステンレス鋼板
US11326236B2 (en) 2017-02-23 2022-05-10 Nippon Steel Stainless Steel Corporation Black ferrite-based stainless steel sheet
JP2018135591A (ja) * 2017-02-23 2018-08-30 日新製鋼株式会社 黒色フェライト系ステンレス鋼板
JP6307188B1 (ja) * 2017-02-23 2018-04-04 日新製鋼株式会社 黒色フェライト系ステンレス鋼板
JP2018168415A (ja) * 2017-03-29 2018-11-01 新日鐵住金ステンレス株式会社 フェライト系ステンレス鋼
JP2019173072A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびその製造方法、ならびに燃料電池用部材
JP2019173074A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
JP2019173075A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
JP2019173073A (ja) * 2018-03-27 2019-10-10 日鉄ステンレス株式会社 フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
EP3778959A4 (en) * 2018-03-27 2022-03-09 NIPPON STEEL Stainless Steel Corporation FERRITIC STAINLESS STEEL AND METHOD OF PRODUCTION THEREOF, FERRITIC STAINLESS STEEL SHEET AND METHOD OF PRODUCTION THEREOF, AND FUEL CELL ELEMENT
WO2019189174A1 (ja) * 2018-03-27 2019-10-03 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびその製造方法、フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
JP7076258B2 (ja) 2018-03-27 2022-05-27 日鉄ステンレス株式会社 フェライト系ステンレス鋼板およびその製造方法、ならびに燃料電池用部材
EP4036255A1 (en) * 2018-03-27 2022-08-03 NIPPON STEEL Stainless Steel Corporation Ferritic stainless steel and method for manufacturing same, ferritic stainless steel sheet and method for manufacturing same, and fuel cell member
US11667986B2 (en) 2018-03-27 2023-06-06 Nippon Steel Stainless Steel Corporation Ferritic stainless steel and method for manufacturing same, ferritic stainless steel sheet and method for manufacturing same, and fuel cell member
EP4223888A3 (en) * 2018-03-27 2023-09-13 NIPPON STEEL Stainless Steel Corporation Ferritic stainless steel and method for manufacturing same, ferritic stainless steel sheet and method for manufacturing same, and fuel cell member
JP2020063499A (ja) * 2018-10-19 2020-04-23 日鉄ステンレス株式会社 ステンレス鋼
JP7296710B2 (ja) 2018-10-19 2023-06-23 日鉄ステンレス株式会社 ステンレス鋼
JP2020100866A (ja) * 2018-12-21 2020-07-02 日鉄ステンレス株式会社 耐水素脆性と耐低温脆性に優れたＣｒ系ステンレス鋼

Also Published As

Publication number Publication date
KR20150110762A (ko) 2015-10-02
JP5837258B2 (ja) 2015-12-24
CN105074035B (zh) 2018-02-16
KR101663207B1 (ko) 2016-10-06
JPWO2014157578A1 (ja) 2017-02-16
CN105074035A (zh) 2015-11-18

Similar Documents

Publication Publication Date Title
JP5837258B2 (ja) 研磨後の表面耐食性に優れるフェライト系ステンレス鋼及びその製造方法
JP6302690B2 (ja) 研磨後の耐食性に優れたフェライト系ステンレス鋼
KR102504491B1 (ko) 강판 및 법랑 제품
JP2010159487A (ja) 耐銹性に優れた高純度フェライト系ステンレス鋼およびその製造方法
JP6196453B2 (ja) 耐スケール剥離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
JP2009197251A (ja) 延性に優れる高強度鋼板およびその製造方法
US10030282B2 (en) Ferrite-based stainless steel plate having excellent resistance against scale peeling, and method for manufacturing same
JP2008001945A (ja) 耐発銹性と加工性に優れた光輝焼鈍仕上げフェライト系ステンレス鋼板およびその製造方法
WO2010008019A1 (ja) 連続鋳造鋳片およびその製造方法
JP2021508771A (ja) 加工後耐食性に優れた亜鉛合金めっき鋼材及びその製造方法
US10174430B2 (en) Si-containing high strength cold rolled steel sheet, method of producing the same, and automotive members
JP5777387B2 (ja) 二相ステンレス鋼の光輝焼鈍方法
TWI750077B (zh) 肥粒鐵系不鏽鋼材料及其製造方法
JP7341016B2 (ja) フェライト系ステンレス冷延鋼板
JP2020509173A (ja) 表面品質に優れた高炭素熱延鋼板及びその製造方法
JP2020504238A (ja) 加工部耐食性に優れたアルミニウム系合金めっき鋼板
JP2011231391A (ja) 表面性状に優れた高Ｓｉ含有鋼板およびその製造方法
JP5375653B2 (ja) 無方向性電磁鋼板の製造方法
JP5487778B2 (ja) Ｍｏ無添加で強度の優れた浸炭用鋼及びこれを用いた浸炭部品
KR101735003B1 (ko) 내식성이 향상된 린 듀플렉스 스테인리스강 및 이의 제조 방법
JP6505415B2 (ja) 加工性と耐食性に優れたＦｅ−Ｃｒ−Ｎｉ系合金材料の表面処理方法
JP2022041426A (ja) オーステナイト系ステンレス鋼板およびその製造方法
US20240018617A1 (en) Thin steel sheet
KR20140083166A (ko) 페라이트계 스테인리스강 및 그 제조방법
TWI762248B (zh) 沃斯田鐵系不鏽鋼

Legal Events

Date Code Title Description
WWE Wipo information: entry into national phase

Ref document number: 201480018150.3

Country of ref document: CN

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 14773080

Country of ref document: EP

Kind code of ref document: A1

DPE1 Request for preliminary examination filed after expiration of 19th month from priority date (pct application filed from 20040101)
ENP Entry into the national phase

Ref document number: 2015508733

Country of ref document: JP

Kind code of ref document: A

ENP Entry into the national phase

Ref document number: 20157023090

Country of ref document: KR

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 14773080

Country of ref document: EP

Kind code of ref document: A1