EP2554701B1 - Ferritic stainless steel sheet superior in surface glossiness and corrosion resistance and method for producing same - Google Patents

Ferritic stainless steel sheet superior in surface glossiness and corrosion resistance and method for producing same Download PDF

Info

Publication number
EP2554701B1
EP2554701B1 EP11762738.0A EP11762738A EP2554701B1 EP 2554701 B1 EP2554701 B1 EP 2554701B1 EP 11762738 A EP11762738 A EP 11762738A EP 2554701 B1 EP2554701 B1 EP 2554701B1
Authority
EP
European Patent Office
Prior art keywords
corrosion resistance
steel sheet
stainless steel
ferritic stainless
good
Prior art date
Legal status (The legal status 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 status listed.)
Active
Application number
EP11762738.0A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP2554701A1 (en
EP2554701A4 (en
Inventor
Masaharu Hatano
Akihito Yamagishi
Shigenori Takahata
Eiichiro Ishimaru
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Stainless Steel Corp
Original Assignee
Nippon Steel and Sumikin Stainless Steel Corp
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 Nippon Steel and Sumikin Stainless Steel Corp filed Critical Nippon Steel and Sumikin Stainless Steel Corp
Publication of EP2554701A1 publication Critical patent/EP2554701A1/en
Publication of EP2554701A4 publication Critical patent/EP2554701A4/en
Application granted granted Critical
Publication of EP2554701B1 publication Critical patent/EP2554701B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous 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
    • C22C38/02—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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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 an alloy-saving type ferritic stainless steel sheet which is excellent in surface glossiness and corrosion resistance and a method for producing the same.
  • a ferritic stainless steel sheet is extensively used in household electrical appliances, kitchen equipments, and other fields in which corrosion resistance and surface quality in an indoor environment are demanded.
  • SUS430LX and SUS430J1L in the JIS standard may be mentioned.
  • NPLT 1 describes representative examples SUS430LX and SUS430J1L which are excellent in corrosion resistance.
  • Such a ferritic stainless steel reduces the C and N, contains Cr: 16 to 20%, Nb: 0.3 to 0.6%, and Ti and trace amounts of Cu and Mo added compositely to prevent deterioration of the surface properties due to pitting or rusting.
  • ferritic stainless steel sheet to which Nb, Ti, etc. have been added has had the defect of being inferior in surface glossiness compared with other ferritic stainless steel sheet (SUS430) in the No. 3D finished or No. 2B finished products prescribed in JIS G 4305 and G 4307.
  • PLT 1 discloses the method of production of cold rolled steel strip which is excellent in surface glossiness by the control of the amount of oxide scale formation in annealing a ferritic stainless steel to which Ti, Nb, etc. are added.
  • PLT 2 discloses the method of descaling cold rolled steel strip and the method of production of stainless cold rolled steel strip which is excellent in glossiness and corrosion resistance which prescribes the step of neutral salt electrolysis-nitrate electrolysis.
  • PLT 3 discloses the method of production of high glossiness stainless steel strip which controls the roughness of the work roll and lubrication conditions in cold rolling.
  • the above-mentioned ferritic stainless steel sheet is excellent economically to an austenitic stainless steel sheet which contains a large amount of Ni - which has remarkably risen in price in recent years.
  • Ni - which has remarkably risen in price in recent years.
  • SUS430LX and SUS430J1L will also have economically sufficient in the future.
  • PLT 4 and PLT 5 disclose a ferritic stainless steel which proactively adds P so as to improve the weather resistance, corrosion resistance, and crevice corrosion resistance.
  • PLT 4 is a high Cr and P ferritic stainless steel which contains Cr: over 20% to 40% and P: over 0.06% to 0.2%.
  • PLT 5 is a P ferritic stainless steel which contains Cr: 11% to less than 20% and P: over 0.04% to 0.2%.
  • P becomes a factor inhibiting manufacturability, workability, and weldability.
  • the inventors have disclosed a ferritic stainless steel which is improved in corrosion resistance by utilizing trace elements - without relying on alloying of Cr or Mo from the viewpoint of economy.
  • PLT 6 is a ferritic stainless steel which contains Cr: 13 to 22% and Sn: 0.001 to 1%, reduces the C, N, Si, Mn, and P, and adds Ti: 0.08 to 0.35% as a stabilizing element.
  • these literatures do not study the effects on the surface glossiness at all, as explained above.
  • NPLT 1 Stainless Steel Handbook, 3rd Edition, P532
  • the present invention has as its theme to obtain a corrosion resistance which is not different from SUS430LX or SUS430J1L by an amount of Cr of less than 16% and strikingly improve the surface glossiness in alloy-saving type ferritic stainless steel sheet and has as its object the provision of alloy-saving type ferritic stainless steel sheet and a method for producing the same which realize this.
  • the inventors engaged in in-depth studies to solve the above problem. As a result, the inventors obtained the following new findings which are the effect of improvement of corrosion resistance due to the addition of Sn and, in addition, and the relationship between the addition of the stabilizing elements Nb and Ti and the surface glossiness in ferritic stainless steel with an amount of Cr of less than 16%, and thereby completed the present invention.
  • the gist of the present invention obtained based on the above findings (a) to (g), is as follows:
  • the remarkable effect is exhibited of obtaining an alloy saving type ferritic stainless steel sheet which is excellent in surface glossiness and corrosion resistance which does not rise in alloy cost or manufacturing cost and therefore is excellent in economy.
  • the steel sheet has a corrosion resistance no different from SUS430LX and SUS430J1L, and remarkably improves the surface glossiness.
  • Si is sometimes added as a deoxidizing element.
  • Si is a solution strengthening element.
  • the upper limit is 1.0%.
  • the lower limit of the Si content is 0.01%. If considering the workability and manufacturing cost, the lower limit is preferably 0.05%.
  • the upper limit of the content is 1.5%. From the viewpoint of the corrosion resistance, the less the content of Mn is, the better characteristics are presented.
  • the upper limit is preferably 1.0%, more preferably 0.3%, still more preferably 0.2%. Further, excessive reduction leads to an increase in the refining cost, so the lower limit of the content of Mn is 0.01%. Preferably, considering the corrosion resistance and the manufacturing cost, the lower limit should be 0.05%.
  • the upper limit of the content is 0.05%. From the viewpoint of the manufacturability and weldability, the less the content of P is, the better characteristics are presented.
  • the upper limit is preferably 0.04%, more preferably 0.03%. Further, an excessive reduction leads to an increase in the refining costs, so the lower limit of the content of P is 0.005%. More preferably, considering the manufacturing cost, it should be 0.01%.
  • S is an impurity element. It inhibits corrosion resistance and hot workability. The less the content of S is, the better characteristics are presented.
  • the upper limit of the content of S is 0.01%. From the viewpoint of the corrosion resistance or hot workability, the less the content of S is, the better characteristics are presented.
  • the upper limit is preferably 0.005%, more preferably 0.003%, still more preferably 0.002%.
  • the lower limit of the content is 0.0001%. More preferably, considering the corrosion resistance and manufacturing cost, the lower limit should be 0.0002%.
  • Cr is an element of ferritic stainless steel. It is also an essential element for securing the corrosion resistance. To secure the corrosion resistance of the present invention, the lower limit is 12%. The upper limit is 16% from the viewpoint of economy compared with SUS430LX. Considering the corrosion resistance and the amount of addition of Sn, it is preferably 13 to 15%.
  • the upper limit is preferably 0.02%, more preferably 0.012%. Further, excessive reduction leads to an increase in the refining cost, so preferably the lower limit is 0.001%. More preferably, considering the corrosion resistance and manufacturing cost, the content should be 0.005%.
  • Nb is an essential element for improving the corrosion resistance and, in addition, improving the surface gloss in the trace Sn steel of the present invention.
  • the above effect is expressed from 0.05% or more.
  • the upper limit is 0.3%.
  • Lhe content is 0.1 to 0.2%.
  • Ti functions as a stabilizing element which immobilizes the C and N and also is an essential element for improvement of the corrosion resistance.
  • the above effect is expressed from 0.03%.
  • the upper limit is 0.15%.
  • the content is 0.05 to 0.1%.
  • the lower limit of the content is 0.005%.
  • the upper limit of the content of Al is 0.5%. From the viewpoint of the workability, toughness, and weldability, the less the content of Al is, the better characteristics are presented.
  • the upper limit is preferably 0.1%, more preferably 0.05%, still more preferably 0.03%. Further, considering the refining cost, the lower limit of the content is more preferably 0.01%.
  • Sn is an essential element for securing the corrosion resistance which is targeted by the present invention without relying on alloying of Cr and Mo and addition of the rare elements Ni, Co, etc.
  • the lower limit of the content of Sn is 0.01%.
  • the content is preferably 0.05% or more, more preferably 0.1% or more.
  • the upper limit is 1.0%.
  • the upper limit of the content is 0.5% or less, more preferably 0.3%, still more preferably 0.2%.
  • Nb and Ti are added in the above ranges.
  • the amounts of addition should satisfy 1 ⁇ Nb/Ti ⁇ 3.5 to obtain the corrosion resistance and the surface glossiness which are targeted by the present invention.
  • Nb/Ti ⁇ 1 surface gloss due to the Ti-based inclusions or Ti-based oxides decreases.
  • 3.5 ⁇ Nb/Ti surface gloss due to the internal oxidation or grain boundary oxidation caused by the rise of the hot rolling heating temperature and annealing temperature decreases.
  • the more preferable range is 1.5 ⁇ Nb/Ti ⁇ 3 considering the corrosion resistance and surface glossiness which are targeted by the present invention.
  • Ni, Cu, Mo, V, Zr, and Co are elements which improve the corrosion resistance due to a synergistic effect with Sn and may be added in accordance with need.
  • the contents When added, the contents are the 0.01% or more where this effect is exhibited, preferably 0.02% or more. More preferably, the contents are 0.05% where the effect is more remarkable. However, if over 0.5%, a rise in the material cost or a decrease in the surface glossiness occurs, so the upper limits of the contents are 0.5%. Since these elements are rare, in case of adding these elements, the preferable ranges of Ni and Cu are 0.1 to 0.4%, while the preferable range of Mo is 0.1 to 0.3%. The preferable ranges of V, Zr, and Co are 0.02 to 0.3%.
  • Mg forms Mg oxides in the molten steel together with Al and acts as a deoxidant and also acts as nuclei for precipitation of TiN.
  • TiN forms the nuclei for solidification of the ferrite phase in the solidification process.
  • By promoting the crystallization of TiN it is possible to cause the fine formation of the ferrite phase at the time of solidification.
  • By refining the solidified structure it is possible to prevent surface defects due to ridging or roping or other coarse solidified structures of the product.
  • it causes improvement of the workability. Therefore, it may be added as needed.
  • the content is 0.0001% or more for realizing these effects. However, if over 0.005%, the manufacturability deteriorates, so the upper limit is 0.005%.
  • the content is 0.0003 to 0.002%.
  • B is an element which improves the hot workability and the secondary workability. Addition to ferritic stainless steel is effective, so it may be added as needed. When added, the content is 0.0003% or more for realizing these effects. However, excessive addition leads to a decrease in the elongation, so the upper limit is 0.005%. Preferably, considering the material cost and workability, the content is 0.0005 to 0.002%.
  • Ca is an element which improves the hot workability and the cleanliness of the steel and may be added as needed.
  • the content is 0.0003% or more for realizing these effects.
  • the upper limit is 0.005%.
  • the content is 0.0003 to 0.0015%.
  • a slab of steel which has the ingredients which are shown in the above section [I] was inserted in a hot rolling heating furnace and heated.
  • the extraction temperature of the slab from the hot rolling heating furnace was 1080°C or more so as to secure an amount of scale formation for removing inclusions at the surface layer of the cast slab which would lead to scabs.
  • the amount of scale formation should be, converted to scale thickness, 0.2 mm or more.
  • the upper limit of the extraction temperature was 1190°C to suppress the formation of MnS or CaS which form starting points of rust and stabilize Ti-based carbon sulfides (for example Ti 4 C 2 S 2 ). If considering securing the corrosion resistance and the surface gloss which are targeted by the present invention, the extraction temperature is preferably 1140 to 1180°C.
  • the coiling temperature after hot rolling is 500°C or more so as to suppress surface defects during coiling. If the coiling temperature is less than 500°C, the spraying of water after hot rolling causes shape defects in the hot rolled steel strip and induces surface defects at the time of uncoiling or running operations.
  • the coiling temperature is 700°C or less so as to suppress the growth of internal oxides or grain boundary oxidation which leads to a decrease in gloss. Over 700°C, precipitates which contain Ti or P easily form and are liable to lead to a decrease in corrosion resistance. If considering securing the surface gloss and corrosion resistance which are targeted by the present invention, the coiling temperature is preferably 550 to 650°C.
  • the sheet After coiling in hot rolling, the sheet is cold rolled. At this time, before the cold rolling, the hot rolled sheet may also be annealed. Further, the cold rolling may be performed once, or twice or more. However, when cold rolling twice or more, process annealing is performed between the cold rolling operations.
  • the annealing temperature is preferably 1050°C or less. Further, the lower limit of the annealing temperature is preferably the recrystallization temperature of the steel (850°C or so).
  • the "recrystallization temperature” means the temperature where new strain-free crystal grains are formed from the rolled worked structure. In the case of performing process annealing between the cold rolling operations, it is preferable to use a similar temperature range.
  • the conditions of the cold rolling are not particularly limited.
  • the finish annealing after the cold rolling is preferably performed at 980°C or less by considering the surface gloss. As explained above, the lower the annealing temperature, the more the internal oxidation and grain boundary oxidation are suppressed. It is advantageous for improvement of the surface gloss. Therefore, the lower limit is preferably the recrystallization temperature of 850°C.
  • the pickling method is not particularly limited. There is no problem even if performed by a method which is commonly used industrially. For example, there are dipping in an alkali salt bath + electrolytic pickling + dipping in nitrofluoric acid and dipping in an alkali salt bath + electrolytic pickling. The electrolytic pickling may be performed by neutral salt electrolysis, nitric acid electrolysis, etc.
  • a ferritic stainless steel which has the ingredients of Table 1 was smelted, hot rolled by an extraction temperature of 1150 to 1220°C, and coiled by a coiling temperature of 480 to 750°C to obtain hot rolled steel sheet of a thickness of 4.0 to 6.0 mm.
  • the hot rolled steel sheet was annealed, or not, and was cold rolled once or twice interspaced by process annealing to produce 0.4 to 1.0 mm thick cold rolled steel sheet.
  • the obtained cold rolled steel sheet was treated by finish annealing at a temperature of completion of recrystallization of 870 to 1020°C and was treated by ordinary pickling to obtain the No. 2B product in surface specifications prescribed in JIS G 4307.
  • the surface gloss was evaluated by measuring the gloss 45° Gloss value (Gs45°) in the rolling direction of the steel sheet (0°) and in the direction perpendicular to the rolling (90°) prescribed in JIS Z 8741.
  • the corrosion resistance was evaluated by preparing samples of steel sheets (thickness x 100 mm square) of No. 2B surfaces and #600 polished surfaces and running tests dipping them in a 80°C, 0.5% NaCl aqueous solution for 168 hr and salt spray tests based on JIS Z 2371 (168 hr continuous spray test).
  • Test No. 8, 9, 15, and 16 have the ingredients which are prescribed in the present invention, but deviate from the method of production according to the present invention (extraction temperature and coiling temperature). These steel sheets satisfy the corrosion resistance or gloss which is targeted by the present invention, but the gloss is inferior to other examples of the present invention.
  • Test No. 22 to 29 are the production method which is prescribed in the present invention, but using ingredients are deviated from that of the present invention. These steel sheets cannot give both the surface gloss and corrosion resistance which are targeted in the present invention.
  • FIG. 1 and FIG. 2 show the relationship between the amounts of Nb/Ti and the surface gloss in the examples.
  • the surface gloss which is targeted by the present invention that is, Gs45°(0°) of 610 or more and Gs45°(90°) of 520 or more corresponding to SUS430LX, it is important to obtain the ranges of ingredients according to the present invention being 1 ⁇ Nb/Ti ⁇ 3.5.
  • an alloy-saving type ferritic stainless steel excellent in surface gloss and corrosion resistance which is economically excellent without rising in alloy cost or manufacturing cost, has a corrosion resistance of SUS430LX or SUS430J1L, and is strikingly improved in surface gloss.

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)
EP11762738.0A 2010-03-29 2011-03-22 Ferritic stainless steel sheet superior in surface glossiness and corrosion resistance and method for producing same Active EP2554701B1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2010076099 2010-03-29
JP2010239851 2010-10-26
PCT/JP2011/057512 WO2011122513A1 (ja) 2010-03-29 2011-03-22 表面光沢と耐銹性に優れたフェライト系ステンレス鋼板およびその製造方法

Publications (3)

Publication Number Publication Date
EP2554701A1 EP2554701A1 (en) 2013-02-06
EP2554701A4 EP2554701A4 (en) 2015-04-29
EP2554701B1 true EP2554701B1 (en) 2016-06-29

Family

ID=44712212

Family Applications (1)

Application Number Title Priority Date Filing Date
EP11762738.0A Active EP2554701B1 (en) 2010-03-29 2011-03-22 Ferritic stainless steel sheet superior in surface glossiness and corrosion resistance and method for producing same

Country Status (9)

Country Link
US (1) US20130017116A1 (zh)
EP (1) EP2554701B1 (zh)
JP (1) JP5709845B2 (zh)
KR (1) KR101536291B1 (zh)
CN (1) CN102822373B (zh)
BR (1) BR112012024625B1 (zh)
ES (1) ES2581315T3 (zh)
TW (1) TWI461547B (zh)
WO (1) WO2011122513A1 (zh)

Families Citing this family (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5745345B2 (ja) * 2011-06-16 2015-07-08 新日鐵住金ステンレス株式会社 熱間加工性と耐銹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
JP5804792B2 (ja) * 2011-06-16 2015-11-04 新日鐵住金ステンレス株式会社 熱間加工性と耐銹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
JP6071608B2 (ja) 2012-03-09 2017-02-01 新日鐵住金ステンレス株式会社 耐酸化性に優れたフェライト系ステンレス鋼板
JP6025362B2 (ja) * 2012-03-29 2016-11-16 新日鐵住金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
JP5793459B2 (ja) 2012-03-30 2015-10-14 新日鐵住金ステンレス株式会社 加工性に優れた耐熱フェライト系ステンレス冷延鋼板、冷延素材用フェライト系ステンレス熱延鋼板及びそれらの製造方法
JP5716054B2 (ja) * 2012-07-13 2015-05-13 新日鐵住金ステンレス株式会社 酸化皮膜の電気伝導性と密着性に優れたフェライト系ステンレス鋼板
KR101673218B1 (ko) * 2012-09-24 2016-11-07 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스강
BR112015009634B1 (pt) * 2012-10-30 2019-08-20 Nippon Steel & Sumikin Stainless Steel Corporation Aços inoxidáveis ferríticos, seus métodos de produção e elementos de sistema de escapamento
JP5843982B2 (ja) * 2013-02-04 2016-01-13 新日鐵住金ステンレス株式会社 加工性に優れたフェライト系ステンレス鋼板およびその製造方法
EP2980251B1 (en) * 2013-03-27 2017-12-13 Nippon Steel & Sumikin Stainless Steel Corporation Hot-rolled ferritic stainless-steel plate, process for producing same, and steel strip
CN106255772B (zh) * 2014-04-30 2018-09-07 杰富意钢铁株式会社 高强度容器用钢板及其制造方法
JP6179485B2 (ja) * 2014-08-14 2017-08-16 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼板
JP6410543B2 (ja) * 2014-09-29 2018-10-24 新日鐵住金ステンレス株式会社 穴広げ性に優れたフェライト系ステンレス鋼鈑及びその製造方法
CN106574350A (zh) * 2014-09-29 2017-04-19 新日铁住金不锈钢株式会社 扩孔性优异的铁素体系不锈钢板及其制造方法
JP6573459B2 (ja) * 2015-02-25 2019-09-11 日鉄ステンレス株式会社 穴拡げ性に優れたフェライト系ステンレス鋼鈑及びその製造方法
WO2016068291A1 (ja) * 2014-10-31 2016-05-06 新日鐵住金ステンレス株式会社 耐排ガス凝縮水腐食性とろう付け性に優れたフェライト系ステンレス鋼及びその製造方法
WO2016068139A1 (ja) 2014-10-31 2016-05-06 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板、鋼管およびその製造方法
JP6159775B2 (ja) 2014-10-31 2017-07-05 新日鐵住金ステンレス株式会社 耐排ガス凝縮水腐食性とろう付け性に優れたフェライト系ステンレス鋼及びその製造方法
JP6323619B2 (ja) * 2015-09-25 2018-05-16 新日鐵住金株式会社 固体高分子形燃料電池用カーボンセパレータ、固体高分子形燃料電池セル、および固体高分子形燃料電池
JP6005234B1 (ja) * 2015-09-29 2016-10-12 日新製鋼株式会社 疲労特性に優れた高強度ステンレス鋼板およびその製造方法
EP3541202B1 (en) * 2016-11-16 2024-02-28 The Coca-Cola Company Taste improvement using miracle fruit for juice from disease impacted fruit
CN108273848B (zh) * 2018-01-30 2018-11-27 北京信达盛包装材料有限公司 一种双暗面铝箔及其制备方法
CN109011281A (zh) * 2018-06-26 2018-12-18 苏州海马消防设备制造有限公司 一种新型不锈钢消防水龙头
JP7186601B2 (ja) * 2018-12-21 2022-12-09 日鉄ステンレス株式会社 高圧水素ガス用機器の金属材料として用いるＣｒ系ステンレス鋼
KR102370505B1 (ko) * 2020-04-28 2022-03-04 주식회사 포스코 내식성이 향상된 페라이트계 스테인리스강 및 이의 제조방법

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61288021A (ja) 1985-06-13 1986-12-18 Kawasaki Steel Corp 表面光沢に優れたフエライト系ステンレス冷延鋼帯の製造方法
JP2749723B2 (ja) 1990-12-28 1998-05-13 川崎製鉄株式会社 光沢、白色度および耐食性に優れたステンレス冷延鋼帯の製造方法
JP2675957B2 (ja) 1992-02-25 1997-11-12 川崎製鉄株式会社 耐候性、耐銹性に優れた高Ｃｒ，Ｐ添加フェライト系ステンレス鋼
JP2880906B2 (ja) 1993-05-19 1999-04-12 川崎製鉄株式会社 耐候性、耐隙間腐食性に優れたフェライト系ステンレス鋼
JPH07150288A (ja) * 1993-10-05 1995-06-13 Nippon Steel Corp 表面性状の良好なＳｎ含有高強度熱延鋼板およびその製造方法
JP3425706B2 (ja) 1995-03-07 2003-07-14 Ｊｆｅスチール株式会社 高光沢ステンレス鋼帯の製造方法
JPH10280035A (ja) * 1997-04-11 1998-10-20 Nippon Steel Corp 加工性と耐熱性に優れた高純フェライト系ステンレス熱延鋼帯の製造方法
JP2001288533A (ja) * 2000-03-31 2001-10-19 Nippon Steel Corp 溶接熱影響部の硬化および軟化が小さい鋼材およびその製造方法
JP4390961B2 (ja) * 2000-04-04 2009-12-24 新日鐵住金ステンレス株式会社 表面特性及び耐食性に優れたフェライト系ステンレス鋼
JP3989790B2 (ja) * 2002-07-30 2007-10-10 新日鐵住金ステンレス株式会社 プレス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
JP4519505B2 (ja) * 2004-04-07 2010-08-04 新日鐵住金ステンレス株式会社 成形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
CA2777715C (en) * 2006-05-09 2014-06-03 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel excellent in resistance to crevice corrosion
CN101397638A (zh) * 2007-09-25 2009-04-01 宝山钢铁股份有限公司 一种汽车尾气排放系统用铁素体不锈钢
JP4651682B2 (ja) 2008-01-28 2011-03-16 新日鐵住金ステンレス株式会社 耐食性と加工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
JP5274074B2 (ja) * 2008-03-28 2013-08-28 新日鐵住金ステンレス株式会社 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板
JP5297713B2 (ja) * 2008-07-28 2013-09-25 新日鐵住金ステンレス株式会社 加熱後耐食性に優れた自動車排気系部材用省合金型フェライト系ステンレス鋼

Also Published As

Publication number Publication date
TWI461547B (zh) 2014-11-21
TW201139698A (en) 2011-11-16
BR112012024625B1 (pt) 2019-01-08
CN102822373A (zh) 2012-12-12
KR101536291B1 (ko) 2015-07-13
JP5709845B2 (ja) 2015-04-30
KR20120127737A (ko) 2012-11-23
BR112012024625A2 (pt) 2016-05-31
CN102822373B (zh) 2016-07-06
EP2554701A1 (en) 2013-02-06
US20130017116A1 (en) 2013-01-17
ES2581315T3 (es) 2016-09-05
EP2554701A4 (en) 2015-04-29
WO2011122513A1 (ja) 2011-10-06
JPWO2011122513A1 (ja) 2013-07-08

Similar Documents

Publication Publication Date Title
EP2554701B1 (en) Ferritic stainless steel sheet superior in surface glossiness and corrosion resistance and method for producing same
EP2687617B1 (en) High-purity ferritic stainless steel sheet with excellent corrosion resistance and anti-glare properties
EP2677055B1 (en) High-purity ferritic stainless steel sheet having excellent oxidation resistance and high-temperature strength, and method for producing same
TWI516614B (zh) Fat iron stainless steel
KR101705135B1 (ko) 페라이트계 스테인리스 강판
TWI638055B (zh) 肥粒鐵系不銹鋼板
EP2980251A1 (en) Hot-rolled ferritic stainless-steel plate, process for producing same, and steel strip
CN107835865B (zh) 铁素体系不锈钢热轧钢板和热轧退火板以及它们的制造方法
JP5862846B2 (ja) フェライト系ステンレス鋼およびその製造方法
KR102286876B1 (ko) 페라이트계 스테인리스 강판 및 그의 제조 방법
KR101532857B1 (ko) 내압 강도가 높고 가공성이 우수한 에어로졸 캔 보텀용 강판 및 그 제조 방법
JP6411881B2 (ja) フェライト系ステンレス鋼およびその製造方法
EP3040427A1 (en) High-strength hot-rolled plated steel sheet and method for manufacturing same
JP4784364B2 (ja) 除錆性および耐発銹性に優れたフェライト系ステンレス鋼板
JP5804792B2 (ja) 熱間加工性と耐銹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
TWI522480B (zh) A method for producing a film for tin plating and a film for tin plating
KR20140083166A (ko) 페라이트계 스테인리스강 및 그 제조방법
JP7269470B2 (ja) 二相ステンレス鋼およびその製造方法
WO2022049796A1 (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
KR101621052B1 (ko) 페라이트계 스테인리스강 및 그 제조방법
KR20200066198A (ko) 저농도 황산/염산 복합 응축 분위기에서 내식성을 갖는 강판 및 그 제조방법

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20121024

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

DAX Request for extension of the european patent (deleted)
RA4 Supplementary search report drawn up and despatched (corrected)

Effective date: 20150326

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/28 20060101ALI20150320BHEP

Ipc: C21D 9/46 20060101ALI20150320BHEP

Ipc: C21D 8/02 20060101ALI20150320BHEP

Ipc: C22C 38/00 20060101AFI20150320BHEP

Ipc: B21B 3/02 20060101ALI20150320BHEP

Ipc: C22C 38/54 20060101ALI20150320BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20160108

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 809174

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160715

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602011027769

Country of ref document: DE

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2581315

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20160905

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160929

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20160629

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160930

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 809174

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160629

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20161029

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 7

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: BE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20161031

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602011027769

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

26N No opposition filed

Effective date: 20170330

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160929

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20170322

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 8

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170322

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170322

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170322

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170331

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170331

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170322

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20110322

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160629

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20160629

REG Reference to a national code

Ref country code: DE

Ref legal event code: R081

Ref document number: 602011027769

Country of ref document: DE

Owner name: NIPPON STEEL STAINLESS STEEL CORPORATION, JP

Free format text: FORMER OWNER: NIPPON STEEL & SUMIKIN STAINLESS STEEL CORP., TOKYO, JP

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20230127

Year of fee payment: 13

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20230314

Year of fee payment: 13

Ref country code: IT

Payment date: 20230309

Year of fee payment: 13

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20230404

Year of fee payment: 13

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FI

Payment date: 20240319

Year of fee payment: 14

Ref country code: DE

Payment date: 20240325

Year of fee payment: 14