US20130017116A1 - Ferritic stainless steel sheet excellent in surface gloss and corrosion resistance and method for producing same - Google Patents

Ferritic stainless steel sheet excellent in surface gloss and corrosion resistance and method for producing same Download PDF

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Publication number
US20130017116A1
US20130017116A1 US13/638,108 US201113638108A US2013017116A1 US 20130017116 A1 US20130017116 A1 US 20130017116A1 US 201113638108 A US201113638108 A US 201113638108A US 2013017116 A1 US2013017116 A1 US 2013017116A1
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steel sheet
corrosion resistance
stainless steel
ferritic stainless
surface gloss
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US13/638,108
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Masaharu Hatano
Akihito Yamagishi
Shigenori Takahata
Eiichiro Ishimaru
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Nippon Steel Stainless Steel Corp
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    • 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 due to the price fluctuations in the component element Cr of stainless steel and the rising price of the rare element Nb, it is difficult to say that 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.
  • 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.
  • Nb is a stabilizing element which is effective for appearing an action in improving the corrosion resistance and surface glossiness. In steel to which a trace amount of Sn is added, that action is appeared from 0.05%. However, if adding Nb 0.3% or more, the rise in the hot rolling heating temperature and annealing temperature of the steel material leads to a decrease in the surface gloss due to the oxide scale.
  • Ti has an action as a stabilizing element which immobilizes C and N and, in addition, forms Ti-based carbosulfides (for example, Ti 4 C 2 S 2 ) at the time of heating for hot rolling and suppresses the formation of MnS or CaS which form starting points of rust. In steel to which a trace amount of Sn is added, that action is appeared from 0.03%. However, if, adding Ti 0.15% or more, scabs due to inclusions and concentration of Ti in the oxide film cause a decrease in surface glossiness.
  • Ti-based carbosulfides for example, Ti 4 C 2 S 2
  • the extraction temperature after heating for hot rolling is a temperature for securing the amount of scale formation for removing inclusions at the cast slab surface layer which induce scabs and for forming Ti-based carbon sulfides (for example, Ti 4 C 2 S 2 ) to suppress the formation of MnS or CaS which forms rust.
  • Ti-based carbon sulfides for example, Ti 4 C 2 S 2
  • setting the temperature 1080 to 1190° C. is effective.
  • the gist of the present invention obtained based on the above findings (a) to (g), is as follows:
  • a ferritic stainless steel sheet which is excellent in surface glossiness and corrosion resistance comprising: by mass %,
  • the steel sheet having the remainder being Fe and unavoidable impurities, and satisfying the relationship of 1 ⁇ Nb/Ti ⁇ 3.5.
  • a method of production of a ferritic stainless steel sheet which is excellent in surface glossiness and corrosion resistance comprising of: heating a slab of stainless steel which contains the steel ingredients described in the above (1) or (2), taking out the slab from the heating furnace at an extraction temperature of 1080 to 1190° C., and hot rolling and coiling the steel sheet at a temperature of 500 to 700° C.
  • 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.
  • FIG. 1 shows the relationship between the Nb/Ti amount and surface glossiness Ga45° (0°).
  • FIG. 2 shows the relationship between the Nb/Ti amount and surface glossiness Ga45° (90°).
  • the upper limit of its content is 0.03%. From the viewpoint of the corrosion resistance, the less the content of C is, the better characteristics are presented.
  • the upper limit is preferably 0.02%, more preferably 0.01%, still more preferably 0.005%. Further, excessive reduction leads to an increase in the refining cost, so the lower limit of the content is 0.001%. Considering the corrosion resistance or manufacturing cost, the lower limit is preferably 0.002%.
  • 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%.
  • the 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 No 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.
  • For the ordinary pickling for example, dipping in an alkali salt bath (430° C.), then treatment by neutral salt electrolysis (50° C., Na 2 SO 4 ) may be used.
  • 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 ⁇ 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.

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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

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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
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