CN102741445A - Highly corrosion-resistant cold-rolled ferrite stainless steel sheet having excellent toughness, and process for production thereof - Google Patents
Highly corrosion-resistant cold-rolled ferrite stainless steel sheet having excellent toughness, and process for production thereof Download PDFInfo
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 64
- 239000010935 stainless steel Substances 0.000 title claims abstract description 62
- 238000000034 method Methods 0.000 title claims abstract description 26
- 230000008569 process Effects 0.000 title claims abstract description 5
- 238000004519 manufacturing process Methods 0.000 title claims description 20
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- 229910000859 α-Fe Inorganic materials 0.000 title abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 76
- 239000010959 steel Substances 0.000 claims description 76
- 239000010960 cold rolled steel Substances 0.000 claims description 41
- 238000000137 annealing Methods 0.000 claims description 37
- 238000005097 cold rolling Methods 0.000 claims description 33
- 238000005096 rolling process Methods 0.000 claims description 20
- 238000005098 hot rolling Methods 0.000 claims description 12
- 238000005554 pickling Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 230000003628 erosive effect Effects 0.000 description 26
- 238000012360 testing method Methods 0.000 description 20
- 230000000694 effects Effects 0.000 description 18
- 238000009863 impact test Methods 0.000 description 11
- 239000000047 product Substances 0.000 description 11
- 238000002474 experimental method Methods 0.000 description 10
- 239000002244 precipitate Substances 0.000 description 9
- 150000004767 nitrides Chemical class 0.000 description 8
- 238000005516 engineering process Methods 0.000 description 7
- 238000011156 evaluation Methods 0.000 description 7
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 5
- 229910000765 intermetallic Inorganic materials 0.000 description 5
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 4
- 230000033228 biological regulation Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
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- 229910001566 austenite Inorganic materials 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
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- 238000010521 absorption reaction Methods 0.000 description 2
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- 229910001068 laves phase Inorganic materials 0.000 description 2
- NICDRCVJGXLKSF-UHFFFAOYSA-N nitric acid;trihydrochloride Chemical compound Cl.Cl.Cl.O[N+]([O-])=O NICDRCVJGXLKSF-UHFFFAOYSA-N 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000011780 sodium chloride Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
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- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- FVMOEFABYNPCDS-UHFFFAOYSA-L calcium;1-(4-carboxy-2,6-dioxocyclohexylidene)propan-1-olate Chemical compound [Ca+2].CCC([O-])=C1C(=O)CC(C(O)=O)CC1=O.CCC([O-])=C1C(=O)CC(C(O)=O)CC1=O FVMOEFABYNPCDS-UHFFFAOYSA-L 0.000 description 1
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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
- C22C38/004—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- 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
-
- 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
- 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
- C22C38/02—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
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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
- C22C38/22—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
- C22C38/26—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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Abstract
Disclosed are: a highly corrosion-resistant cold-rolled ferrite stainless steel sheet having excellent toughness, which is characterized by having a Charpy impact value of 100 J/cm2 or more at -50 DEG C when the ferrite stainless steel sheet has a thickness of 4 mm; and a process for producing the ferrite stainless steel sheet. Specifically disclosed is a highly corrosion-resistant cold-rolled ferrite stainless steel sheet having excellent toughness, which is characterized by comprising (in mass%) 0.020% or less of C, 1.0% or less of Si, 1.0% or less of Mn, 0.06% or less of P, 0.01% or less of S, 18.0-24.0% of Cr, 0.3% or less of Mo, 0.015% or less of Ti, 0.20-0.40% of Al, 0.020% or less of N, Nb in such an amount that the following formula: 10*(C+N) =< Nb <= 0.40% is fulfilled, and Fe and unavoidable impurities which make up the remainder, wherein the contents of the components meet the formula (A). Ti*N <= 8.00*10<-5>...(A).
Description
Technical field
The present invention relates to toughness (toughness) or processibility (workability) also excellent high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet (high-corrosion resistance cold rolled ferritic stainless steel sheet) and method of manufacture thereof.
Background technology
In the stainless steel because its excellent erosion resistance and toughness and austenite stainless steel (austenitic stainless steel) SUS304 (18%Cr-8%Ni) (Japanese Industrial Standards, JIS G 4305) extensively is used.But price is high owing to contain a large amount of Ni for this steel grade.In the ferrite-group stainless steel that does not contain Ni in a large number (ferritic stainless steel),, the SUS436L (18%Cr-1%Mo) (JIS G 4305) that contains Mo is arranged as the steel grade of erosion resistance with the excellence that is equivalent to SUS304.But, because Mo also is the high element of price, so also significantly increase cost (increase in cost) even if only contain 1%.In addition, has enough toughness as not talkative this SUS436L of structure unit (structural member).In addition, SUS430J1L (19%Cr-0.5%Cu-0.4%Nb) (JIS G 4305) is arranged in the ferrite-group stainless steel that does not contain Mo, but it is hard to tell that as structure unit it has enough toughness.
In recent years, seeking to have and the general steel grade SUS430 of stainless steel, erosion resistance that SUS304 is suitable always, and applicable to the excellent ferrite-group stainless steel cold-rolled steel sheet of the low-temperature flexibility of structure unit purposes.
Particularly, need to make the above hot-rolled steel sheet (hot rolled steel sheet) of thickness of slab 6mm from obtaining the viewpoint that thickness of slab surpasses the excellent cold-rolled steel sheet of the low-temperature flexibility of 2mm and the thickness below the 4mm and guarantees cold rolling draft (rolling reduction of cold rolling).Compare with austenite stainless steel, the hot rolling part of ferrite-group stainless steel and cold rolling toughness are relatively poor.The ferrite-group stainless steel hot-rolled steel sheet is used continuous annealing furnace usually; Carry out hot-rolled sheet annealing; But under the inadequate situation of the toughness of hot rolling part, if under the state to the hot-rolled steel sheet additional tension, make its production line through the continuous annealing operation, then the possibility of slab fracture is high more more for thickness of slab.Therefore, in the past since, be mainly 4 ~ 5mm as the thickness of slab of cold rolling ferrite-group stainless steel hot-rolled steel sheet with blank.Therefore, need to improve the toughness of the above ferrite-group stainless steel hot-rolled steel sheet of thickness of slab 6mm.
In addition; Owing to compare with austenite stainless steel; Cheap and the excellent corrosion resistance of ferrite-group stainless steel is so the cold-rolled steel sheet below the thickness of slab 2mm is widely used in galley equipment (kitchen instruments), the home appliance (household electrical appliance) etc.In recent years; Because the decarburization in the steel making technology (steel making process) and the progress of denitride technology (decarburizing and denitrogenation technology); Develop minimizing C that processibility and erosion resistance be further improved and the highly purified ferrite-group stainless steel cold-rolled steel sheet of N, in purposes widely, be processed into complicated shape and the chance used increases gradually.
From such background, the improvement technology of punch process property (the press workability), particularly pull and stretch performance (deep drawability) of ferrite-group stainless steel cold-rolled steel sheet is expected.Often using in the processing of pull and stretch key element, the average r value that improves material is extremely important.
For the improvement of average r value, increase very effect of cold rolling draft, but, need to make the above hot-rolled steel sheet of thickness of slab 6mm from obtaining the cold-rolled steel sheet below the thickness of slab 2mm and guaranteeing the viewpoint of higher cold rolling draft.
Therefore, as stated, when desire increases cold rolling draft in order to improve average r value, need to improve the toughness of the above ferrite-group stainless steel hot-rolled steel sheet of thickness of slab 6mm.
To this; As the flexible technology of improving ferrite-group stainless steel; Disclose a kind of water-heater in the patent documentation 1 and used ferrite series stainless steel plate; It is characterized in that, in quality %, contain below the C:0.020%, Si:0.30 ~ 1.00%, below the Mn:1.00%, below the P:0.040%, below the S:0.010%, Cr:20.0 ~ 28.0%, below the Ni:0.6%, Al:0.03 ~ 0.15%, below the N:0.020%, O:0.0020 ~ 0.0150%, Mo:0.3 ~ 1.5%, Nb:0.25 ~ 0.60%, below the Ti:0.05%; Remainder is made up of Fe and unavoidable impurities, and satisfies 25≤Cr+3.3Mo≤30 and 0.35≤Si+Al≤0.85.
In addition; The ferrite series stainless steel plate of a kind of processibility and tenacity excellent is disclosed in the patent documentation 2; Its chemical constitution is in quality %; Below the C:0.1%, N:0.003 ~ 0.05%, Si:0.03 ~ 1.5%, below the Mn:1.0%, below the P:0.04%, below the S:0.03%, Cr:10 ~ 30%, below the Cu:2%, below the Ni:2%, below the Mo:3%, below the V:1%, Ti:0.02 ~ 0.5%, O (oxygen): 0.001 ~ 0.005%, below the Nb:0.8%, Al:0.001 ~ 0.15%, below the Zr:0.3%, below the B:0.1%, below the Ca:0.003%, Mg: be lower than 0.0005%; Satisfy more than Ti * N:0.0005; Remainder is Fe and can not keep away impurity, and having disperseed with 0.3 ~ 0.5 Mg and the content of Al in the steel is the complex inclusion of inclusion than inclusion that contains Al and Mg (inclusion) and Ti.
But; When the purpose of patent documentation 1 is to guarantee to prevent hot-rolled sheet annealing and this manufacturing property of fracture (productivity) of the steel band when cold rolling; It is the flexible technology of the hot-rolled steel sheet of the thickness of slab 4mm when improving 0 ℃; And owing to contain Mo in a large number, also easy generation makes the intermetallic compound (intermetallic compound) of toughness reduction etc.Therefore, think that then toughness is insufficient if be used for the purposes of the thicker thickness of slab of the object of the invention.
In addition, in the patent documentation 2, Ti is that the decentralised control (dispersion control) of inclusion is also difficult, because of its thickization reduces toughness easily, can not obtain enough toughness.
Patent documentation 1: TOHKEMY 2008-190035 communique
Patent documentation 2: TOHKEMY 2001-020046 communique
Summary of the invention
As previously discussed, in the method that contains Mo, Ti, also fully do not realize the hot-rolled sheet of ferrite-group stainless steel and the tough property improvement of cold-reduced sheet.
Therefore; The objective of the invention is to; Toughness through the thickness of slab 6mm that improves the ferrite-group stainless steel hot-rolled steel sheet significantly when above, thus provide a kind of with in the cold-rolled steel sheet below the thickness of slab 4mm, and-50 ℃ Charpy impact value (charpy impact value) is 100J/cm
2More than be the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet and the method for manufacture thereof of the tenacity excellent of characteristic.
In addition, the object of the present invention is to provide-50 ℃ Charpy impact value of the cold-rolled steel sheet below a kind of thickness of slab 2mm is 100J/cm
2Above, toughness and also excellent high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet and the method for manufacture thereof of processibility, particularly pull and stretch performance.
Contrivers etc. are in order to solve above-mentioned problem, and the Ni, Mo and the erosion resistance that do not contain high price and toughness even the processibility also acquisition methods of the excellent ferrite-group stainless steel cold-rolled steel sheet that contains Nb are furtherd investigate.
At first, to realizing that experimental result of the present invention describes.Below, short of special instruction, the % of chemical ingredients all representes the meaning of quality %.
At first, found out that the thick TiN precipitate that generates from solidification stages exists in the steel that contains as the Ti of the stabilizing element of ferrite-group stainless steel steel, because of the notch effect toughness of this precipitate descends significantly.Therefore, do not sneak into Ti as far as possible, select Nb as stabilizing element, and then various alloys are studied the flexible influence of the ferrite-group stainless steel that contains Nb, the result has noticed Al.Melting 21%Cr-0.25%Nb-hangs down in C, the N steel and makes Al contain 0.03 ~ 0.50% steel, is heated to 1200 ℃ and carries out hot rolling, and coiling temperature is made as 450 ℃, has made the hot-rolled sheet of thickness of slab 7mm.Charpy impact test (Charpy impact test) when the hot-rolled sheet of the thickness of slab 7mm that obtains has been carried out 0 ℃.With its result shown in Fig. 1.The value of the longitudinal axis of Fig. 1 be with the absorption that will obtain by test can value divided by the sectional area of the notch part of shock test sheet, be converted into thus per unit area absorption can value (below, be called Charpy impact value).
In addition, contriver etc. anneal to the hot-rolled steel sheet of above-mentioned thickness of slab 7mm, make hot-roll annealing plate (hot rolled and annealed steel sheet), after the pickling, are cold-rolled to thickness of slab 4mm.Through cold-reduced sheet being carried out further final annealing at 980 ℃, the Charpy impact test when the cold rolled annealed plate of the thickness of slab 4mm that obtains has been carried out-50 ℃.With its result shown in Fig. 2.
The value of the longitudinal axis of Fig. 2 is identical with Fig. 1.
Can know by Fig. 1 and Fig. 2, contain Al, can significantly improve the toughness of cold rolled annealed plate of hot-rolled steel sheet and the thickness of slab 4mm of thickness of slab 7mm through scope 0.20 ~ 0.40%.
Though its reason is still indeterminate, infer it is through containing Al, thereby the O amount in the steel reduced that inclusion minimizing etc. is caused.In addition, the flexible when surpassing 0.40% scope about Al reduces, and thinks because due to the increase of solid solution Al.
Then; In order to estimate Ti, N flexible influence to hot-rolled sheet and cold rolled annealed plate; To in the low C-N steel of the 21%Cr-0.25%Nb-0.25%Al-shown in the table 1, change the steel that Ti, N amount form and carry out melting; Be heated to 1200 ℃ and carry out hot rolling, coiling temperature is made as 450 ℃, make the hot-rolled sheet of thickness of slab 7mm.Charpy impact test when the hot-rolled sheet of the thickness of slab 7mm that obtains is carried out 0 ℃.With its result shown in Fig. 3.In addition, the hot-rolled sheet of above-mentioned thickness of slab 7mm is annealed, make the hot-roll annealing plate, after the pickling, be cold-rolled to till the thickness of slab 4mm.In addition, through cold-reduced sheet being carried out final annealing, thereby make the cold rolled annealed plate of thickness of slab 4mm, under test temperature-50 ℃, carried out Charpy impact test at 980 ℃.Its result is illustrated at Fig. 4.The transverse axis of Fig. 3 and Fig. 4 is represented the long-pending of Ti (%) and N (%), is the value that is equivalent to solubility product (solubility product constant) (below be called " solubility product ").Can know that by Fig. 3 and Fig. 4 Ti (%) * N (%) surpasses 8.0 * 10
-5Scope in, toughness significantly reduces.
In order to investigate its reason; After will grinding the section structure (sectional structure) of experiment 2-4 and hot-rolled sheet of testing 2-5 and cold rolled annealed plate (cold rolled and anneald steel sheet); With chloroazotic acid (aqua regalis) corrosive sample; (SEM) penetrating analyser (energy dispersive X-ray analyzer) with energy dispersion type X with sem (electron scanning microscope) (EDX) observes, analyzes; Its result, (solubility product of Ti and N is 8.00 * 10 to be the experiment 2-4 of H.T. at hot-rolled sheet and cold rolled annealed plate
-5) the steel of sample in to have observed diameter be the small globular Nb carbide (carbide) of 200 ~ 300nm.On the other hand, hot-rolled sheet and cold rolled annealed plate are low flexible experiment 2-5 (solubility product of Ti and N are 9.52 * 10
-5) the steel of sample in observed the Ti nitride (nitride) that a plurality of diameters are 2 ~ 5 μ m thick rectangular-shaped (rectangular solid like).Think that this is because the solubility product of Ti and N surpasses 8.00 * 10
-5The time, separate out Ti nitride and thickization from solidification stages, because of notch effect (notch effect) reduces toughness.
In addition, the hot-rolled sheet thickness of slab that cold rolled annealed plate suited of making thickness of slab 4mm is studied.Use the steel of the experiment 2-2 of table 1, having made thickness of slab through hot rolling is 4 kinds of hot-rolled sheets of 5.0mm, 5.7mm, 6.8mm, 8.0mm.And then, hot-rolled sheet is annealed, after the pickling, carried out cold rolling, final annealing, make the cold rolled annealed plate of thickness of slab 4mm.Charpy impact test when the cold rolled annealed plate of the thickness of slab 4mm that obtains has been carried out-50 ℃.
With these results table 2 illustrate.Experiment 3-2 (the thickness of slab 5.7mm of hot-rolled sheet; Cold rolling draft 30%), experiment 3-3 (the thickness of slab 6.8mm of hot-rolled sheet; Cold rolling draft 41%) and-50 ℃ the Charpy impact value of cold rolled annealed plate of experiment 3-4 (the thickness of slab 8.0mm of hot-rolled sheet, cold rolling draft 50%) be 100J/cm
2More than.On the other hand ,-50 ℃ Charpy impact value of the cold rolled annealed plate of experiment 3-1 (the thickness of slab 5.0mm of hot-rolled sheet, cold rolling draft 20%) is lower than 100J/cm
2After will grinding the section structure of these cold rolled annealed plates, with chloroazotic acid corrosive sample, observe with opticmicroscope, its result has observed in the sample of experiment 3-1 in rolling direction and has been the banded thick recovery organization that stretches.Think that this is that the savings of strain energy becomes insufficient because cold rolling draft is lower than at 30% o'clock, do not have abundant recrystallize in the cold-reduced sheet annealing, become thick recovery organization, thereby toughness descends.
Find by above result of study; From the viewpoint of its erosion resistance with the property made; The content of Cr is made as 18.0 ~ 24.0%, makes on its basis of containing an amount of Al, be controlled in right amount through solubility product ［ Ti% ］ * ［ N% ］ with Ti that contains in the steel and N; The generation of the thick TiN precipitate of separating out from the molten steel stage of important factor that hot-rolled sheet and cold rolled annealed plate toughness reduces can be suppressed to belong to, the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of tenacity excellent can be obtained.The present invention is based on above opinion and accomplishes.
Then, more than 1.30 target with the average r value of the cold rolled annealed plate that it has been generally acknowledged that the well behaved index of pull and stretch, the influence of cold rolling draft is also studied.Use the steel of the experiment 2-2 of table 1, be heated to 1200 ℃ and carry out hot rolling, coiling temperature is made as 450 ℃, the manufacturing thickness of slab is 7 kinds the hot-rolled sheet of 4.0mm, 4.5mm, 5.0mm, 5.5mm, 6.0mm, 7.0mm, 8.0mm.And then, hot-rolled sheet is annealed, after the pickling, carried out cold rolling, final annealing, make the cold rolled annealed plate of thickness of slab 2mm.Become 45 ° direction along rolling direction, with rolling direction, become 90 ° direction with rolling direction from the cold rolled annealed plate of the thickness of slab 2mm that obtains; Cut JIS13 B test film; After each test film being given 15% tension strain, try to achieve the average r value shown in the following formula.
Average r value=(r
L+ 2r
D+ r
C)/4, wherein, r
L, r
D, r
CBe respectively rolling direction, become 45 ° of directions with rolling direction, become the r value of 90 ° of directions with rolling direction.Average r value is big more, and expression pull and stretch performance is more excellent.
These results are illustrated at table 3 and Fig. 5.Making cold rolling draft is to carry out more than 65% in the cold rolling sample, and the average r value that has obtained target is the characteristic more than 1.30.
The present invention is based on above opinion and accomplishes.
That is of the present invention being constructed as follows.
(1) a kind of high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of tenacity excellent; It is characterized in that; In quality %; Below the C:0.020%, below the Si:1.0%, below the Mn:1.0%, below the P:0.06%, below the S:0.01%, Cr:18.0 ~ 24.0%, below the Mo:0.3%, below the Ti:0.015%, Al:0.20 ~ 0.40%, below the N:0.020%; And 10 * (C+N)≤Nb≤0.40%, and component content satisfies following formula (A), and remainder is made up of Fe and unavoidable impurities;
Ti×N≤8.00×10
-5....（A）
Here, each symbol of element is represented the component content (quality %) in the steel.
(2) according to (1) described ferrite-group stainless steel cold-rolled steel sheet, it is characterized in that, in quality %, below the Si:0.5%, below the Mn:0.8%, below the Ti:0.010%.
(3) according to the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of (1) described tenacity excellent,, contain below the C:0.015%, below the N:0.015% in quality %.
(4) according to the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of each described tenacity excellent in (1) ~ (3),, also contain at least one in following group of A and the group B in quality %.
Group A: be selected from below Cu:0.3 ~ 0.8%, Ni:1.0% and in below the Co:1.0% more than a kind
Group B:B:0.0002 ~ 0.0020%
(5) according to the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of each described tenacity excellent in (1) ~ (4), the Charpy impact value the when summer behind the final annealing of above-mentioned cold-rolled steel sheet, ratio impacted characteristic in-50 ℃ is 100J/cm
2More than.
(6) a kind of method of manufacture of high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of tenacity excellent; Be to use steel billet with each described composition in above-mentioned (1) ~ (4); Heat, hot rolling, hot-rolled steel sheet annealing, pickling, cold rolling, final annealing and make the method for ferrite-group stainless steel cold-rolled steel sheet; Wherein, with after the above-mentioned hot rolling and the thickness of the hot-rolled steel sheet before the hot-rolled steel sheet annealing process more than the 6mm.
(7) method of manufacture of the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of basis (6) described tenacity excellent is characterized in that, the Charpy impact value the when summer of above-mentioned hot-rolled steel sheet, ratio impacted characteristic in 0 ℃ is 50J/cm
2More than.
(8) according to the method for manufacture of the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of (6) or (7) described tenacity excellent, it is characterized in that, above-mentioned rolling draft when cold rolling is made as more than 30%.
According to the present invention, can access the high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet of tenacity excellent, it is characterized in that-50 ℃ Charpy impact value during thickness of slab 4mm is 100J/cm
2More than, further be preferably 150J/cm
2More than.
And, can also obtain on above-mentioned flexible improves, processibility also becomes excellent high corrosion resistance ferrite-group stainless steel cold-rolled steel sheet.
Description of drawings
Fig. 1 is the figure of expression Al amount to the influence of 0 ℃ Charpy impact value.
Fig. 2 is the figure of the influence of right-50 ℃ Charpy impact value of expression Al amount.
Fig. 3 is the figure of expression ［ Ti (%) ］ * ［ N (%) ］ to the influence of 0 ℃ Charpy impact value.
Fig. 4 is the figure of the influence of expression ［ Ti (%) ］ * Charpy impact value that ［ N (%) ］ is right-50 ℃.
Fig. 5 is the figure of the relation of cold rolling draft of expression and average r value.
Embodiment
Below, the mode that is used for embodiment of the present invention is elaborated.
The qualification reason of the composition of ferrite-group stainless steel hot-rolled steel sheet of the present invention at first, is described.
Below the C:0.020%
C combines with Cr easily and forms the Cr carbide, if when welding at heat affected zone (heat-affected zone) formation Cr carbide, then will become the reason of grain boundary corrosion (intergranular corrosion), so C is low more good more.Therefore, C is defined as below 0.020%, more preferably below 0.015%.Should explain that when the high grain boundary corrosion of special demands prevents under the situation of performance, the viewpoint from refining cost (refining cost) further is preferably 0.003 ~ 0.010%.
Below the Si:1.0%
Si is as the useful element of reductor (deoxidizing agent).In order to obtain this effect, be preferably more than 0.05%.But, if contain in a large number then reduce toughness.Therefore, Si is made as below 1.0%.More preferably below 0.5%, further be preferably below 0.05 ~ 0.3%.
Below the Mn:1.0%
Mn combines with S in being present in steel, forms the MnS that belongs to dissolvable sulfide (fusible sulfide), and erosion resistance is reduced.Therefore, Mn is below 1.0%.More preferably below 0.8%.Should explain, under the situation of special demands high corrosion resistance, from the viewpoint of refining cost, more preferably below 0.05 ~ 0.6%.
Below the P:0.06%
P is to the deleterious element of erosion resistance, so preferably lower as far as possible.In addition, if surpass 0.06%, then, solution strengthening (solid solution strengthening) reduces owing to making processibility (workability).Therefore P is made as below 0.06%.And,, then be preferably below 0.04% if consider processibility and toughness.
Below the S:0.01%
S is to the deleterious element of erosion resistance, so preferably lower as far as possible, is made as below 0.01%.In order to obtain high corrosion resistance, further be preferably below 0.006%.
Cr：18.0~24.0%
Cr forms passive film (passive film) and the element of raising erosion resistance on the surface.If Cr content is lower than 18.0%, then can not obtain sufficient erosion resistance.On the other hand, if surpass 24.0%, then becoming is easy to generate σ phase embrittlement (sigma phase embrittlement), 475 ℃ of fragility, and toughness descends easily.Therefore, Cr is made as 18.0 ~ 24.0%.And the viewpoint from high corrosion resistance is preferably 20.0 ~ 24.0%.
Below the Mo:0.3%
If contain Mo, then has the effect that improves stainless erosion resistance.If excessively contain, then generate Laves phase thick intermetallic compounds such as (Laves phase), reduce toughness.Therefore, Mo is made as below 0.3%.
Nb：10×（C＋N）~0.40%
Nb will become Nb carbide, Nb nitride or their compound precipitate and innoxious to the deleterious C of erosion resistance, N, have the effect that improves erosion resistance.If but the Nb amount is lower than 10 times of (C+N) amount, then separating out of Nb carbide, Nb nitride or their compound precipitate becomes insufficient, and Cr carbide, Cr nitride or their compound precipitate are separated out, and reduce erosion resistance.Therefore, Nb is defined as more than 10 * (C+N) %.On the other hand, if excessively contain, then generate Laves and equate thick intermetallic compound, toughness descends.Therefore, Nb is made as 10 * (C+N) ~ 0.40%.Be preferably 12 * (C+N) ~ 0.30%.
Wherein, C, N represent the content in the composition separately of quality %.
Ti：0.015%
Ti forms thick nitride, reduces toughness.Therefore, Ti is made as below 0.015%.More preferably be made as below 0.010%.Should explain, under the situation of special demands H.T., further be preferably below 0.005%.
Below the N:0.020%
N reduces toughness through forming nitride with Ti or Nb.Particularly with the situation of Ti coexistence under, generate thick TiN precipitate from the solidification stages of molten steel, significantly reduce because of its notch effect makes toughness.Therefore, N is made as below 0.020%.Should explain, under the situation of special demands high corrosion resistance, be preferably below 0.015%%, more preferably below 0.010%.
Al：0.20~0.40%
Al is the important element among the present invention, has the flexible of raising effect.For for the toughness of the object of the invention, if be lower than 0.20%, then its effect is insufficient.In addition, surpass at 0.40% o'clock, hot workability (hot-workability) descends.Therefore, Al is made as 0.20 ~ 0.40%.In addition, under the situation of special demands H.T., be preferably 0.20 ~ 0.30%.
Ti×N≤8.00×10
-5
As stated, becoming the thick TiN precipitate of the important factor that the toughness of ferrite-group stainless steel hot-rolled steel sheet descends, is to generate from solidification stages.In order to suppress separating out of this TiN, Ti, N are few more good more, and the solubility product of Ti * N is defined as 8.00 * 10
-5Below.Preferably be made as 5.00 * 10
-5Below.Wherein, Ti, N represent the content in the composition separately of quality %.
Remainder beyond the above-mentioned chemical ingredients is Fe and unavoidable impurities.Should explain, as unavoidable impurities, for example can allow below the Mg:0.0020%, below the Ca:0.0020%, below the V:0.10%, but be not limited to these elements.
Ferrite-group stainless steel hot-rolled steel sheet of the present invention will obtain the purpose characteristic owing to the above-mentioned element that must contain, but also can contain following element according to desirable characteristic.And,, do not get rid of yet and contain following composition in addition as long as in the scope of not damaging action effect of the present invention.
Cu：0.3~0.8%
Cu is through containing the element that it can improve erosion resistance, is particularly reducing effective elements aspect the crevice corrosion (crevice corrosion).In order to bring into play this effect, amount is necessary for more than 0.3%.On the other hand, if amount surpasses 0.8%, then hot workability descends.Therefore, Cu is made as 0.3 ~ 0.8%.Be preferably 0.3 ~ 0.5%.But, do not need under the situation of extra high erosion resistance, owing to rising manufacturing cost, it damages economy, so need not contain Cu.
Below the Ni:1.0%
If contain Ni, the effect that prevents because of the decline that contains the hot workability that Cu causes is arranged then.And, have the effect that reduces crevice corrosion.In order to obtain this effect, be preferably more than 0.05%.But it is the high element of price, even and if amount surpass 1.0%, above-mentioned effect is also saturated, reduces hot workability on the contrary.Therefore, Ni is made as below 1.0%.Be preferably 0.05 ~ 0.4%.
Below the Co:1.0%
Co contains the element that it then helps to improve low-temperature flexibility.In order to obtain this effect, be preferably more than 0.05%.But, excessively contain ductility (ductility) descended.Therefore, Co is made as below 1.0%.
B：0.0002~0.0020%
B contains its then anti-secondary processing brittleness (resistance to cold-work embrittlement) effective elements when improving drawing and forming (deep drawing).If be lower than 0.0002%, then can not obtain this effect.On the other hand, excessively contain hot workability and pull and stretch performance (deep drawability) are descended.Therefore, when containing B, preferred 0.0002 ~ 0.0020% scope.
When the toughness of the cold rolled annealed plate (cold rolled and annealed steel sheet) of estimating steel plate of the present invention; The reason of selected-50 ℃ temperature is an environment of considering that steel of the present invention is used as structure at the building materials field of cold district (cold latitudes) in Charpy impact test; Behind the final annealing with cold-rolled steel sheet, the Charpy impact value in the Charpy impact test under-50 ℃ is 100J/cm
2More than be evaluated as good.In addition, with 150J/cm
2More than be evaluated as extremely good.
In addition, the evaluation of the erosion resistance of steel plate is carried out through measure pitting potential like the back saidly according to JIS G 0577, and is good with being evaluated as more than the 180mV vs SCE, is lower than 180mV vsSCE and is evaluated as bad.
In addition, of the back, the processing characteristics behind the final annealing of cold-rolled steel sheet is estimated with average r value, is that average evaluation more than 1.30 is well with this value.
Then, the method for manufacture of ferrite-group stainless steel to invention describes.
Effective method of manufacture of the present invention is that continuously poured (continuous casting) becomes steel billet (slab), and the scope that is heated to 1100 ~ 1300 ℃ is carried out hot rolling, forms coils of hot-rolled steel.If the coil of strip coiling temperature during hot rolling is above 650 ℃; Then batch back carbide precipitate, intermetallic compound, thereby reduce toughness, therefore preferably coiling temperature is made as below 650 ℃; Require preferably coiling temperature to be made as below 450 ℃ under the situation of H.T..In addition; For the cold rolled annealed plate of making the tenacity excellent below the thickness of slab 4mm or the cold rolled annealed plate of toughness below the thickness of slab 2mm and excellent in workability; From guaranteeing the viewpoint of cold rolling draft, the thickness of slab of hot-rolled steel sheet (also abbreviating " hot-rolled sheet " as) is made as more than the 6mm.Further be preferably more than the 7mm.The hot-rolled sheet that obtains is utilized continuous annealing line, pickling line, anneal 900 ~ 1150 ℃ scope, pickling.In the continuous annealing line of hot-rolled sheet, owing to make it pass through continuous annealing line in that hot-rolled sheet is given under the tensile state, so when the toughness of hot-rolled sheet is insufficient, produce the plate fracture sometimes, so the Charpy impact value of the hot-rolled sheet under preferred 0 ℃ is 50J/cm
2More than.
Then, hot-roll annealing plate (steel plate that hot-rolled steel sheet is annealed and obtained) is implemented cold rolling, final annealing, obtain cold rolled annealed plate.
In order to obtain the cold rolled annealed plate of H.T., guarantee that preferably the cold rolling draft when cold rolling adds up to more than 30%, so that the thick recovery organization that in final annealing, stretches along rolling direction is not residual.
In addition, in order to obtain the cold rolled annealed plate of H.T. and high working property, guarantee that preferably cold rolling draft is more than 65%, fully puts aside strain energy.
In addition, final annealing is preferably at the annealing temperature more than 950 ℃.
The method of manufacture of ferrite-group stainless steel hot-rolled steel sheet of the present invention is not limited to said method, can use known method.
Embodiment 1
His-and-hers watches 4-1 carries out melting with the ferrite-group stainless steel of the chemical ingredients shown in the table 4-2, gets the thick steel billet of 250mm with the continuously poured legal system.After these steel billets were heated to 1200 ℃, roughing was thick to 35mm, since 1050 ℃ of finish to gauges; 900 ℃ of end, batching at 500 ℃ is also cooling of web-like, obtains the hot-rolled sheet of thickness of slab 5 ~ 8mm; Take then that (rolling direction is for taking direction; Impact direction is the rolling width direction, and the width of test film is a thickness of slab) each 5 of No. 4 test films of JIS Z 2202 defineds (wherein, with width as the thickness of slab size); According to the regulation of JIS Z 2242, in test temperature: 0 ℃ condition is implemented Charpy impact test.Charpy impact value to 5 test films averages, with 50J/cm
2Be good when above, be lower than 50J/cm
2The time be bad.
In addition, hot-rolled sheet after keeping 80 seconds (top temperature: 1100 ℃) more than 1050 ℃, is implemented naturally cooling annealing, obtain the hot-roll annealing plate.After the hot-roll annealing plate that obtains carried out pickling, be cold-rolled to the thickness of slab shown in the table 5, carry out final annealing at 980 ℃.Take from these cold rolled annealed plates that (rolling direction is for taking direction; Impact direction is the rolling width direction; The width of test film is a thickness of slab) No. 4 test films of JIS Z 2202 defineds are (wherein; Width is made as 4mm) each 5, according to the regulation of JIS Z 2242, in test temperature: implement Charpy impact test under-50 ℃ the condition.Charpy impact value to 5 averages, with 100J/cm
2Above situation is good, is lower than 100J/cm
2Situation be bad.In addition, with 150J/cm
2Above situation is good for extremely.
And, according to JIS G 0577,, in 3.5%NaCl solution, 30 ℃, measure pitting potential (pitting potential) to the test film of taking from cold rolled annealed plate, estimate erosion resistance.Good with being evaluated as more than the 180mV vs SCE, be lower than 180mV vs SCE and be evaluated as bad.
With the result who obtains in the lump table 5 illustrate.As described in Table 5, steel plate No.4 ~ 7,10 ~ 16,18 ~ 21,23 ~ 24,26 ~ 34,36-50 ℃ Charpy impact value are 100J/cm
2More than, toughness is good, and pitting potential is more than 180mV vs SCE, and erosion resistance is also good.On the other hand, the pitting potential of the poor steel plate No.3 of Nb and the poor steel plate No.35 of Cr is lower than 180mV vs SCE, and erosion resistance is bad.In addition, because 0 ℃ Charpy impact value of steel plate No.1,2,8,9,17,22,25 hot-rolled sheet is lower than 50J/cm
2So, the plate fracture might take place during through continuous annealing line under applying tension force, so do not carry out evaluation thereafter.In addition, the solubility product of Ti and N is big, the thickness of slab of hot-rolled steel sheet is 5mm and be the steel plate No.37 that 20% method of manufacture obtains based on cold rolling draft, and its Charpy impact value of-50 ℃ is lower than 100J/cm
2
Embodiment 2
Among the embodiment 2, except the thickness of slab of the cold rolling draft of the cold-rolled steel sheet of embodiment 1 and cold rolled annealed plate, all the other are identical with embodiment 1.Therefore, the steel No. of the table 6 of embodiment 2 is identical with the steel No. shown in table 4-2 and the table 5 with the table 4-1 of embodiment 1.That is, the hot-roll annealing plate of embodiment 1 carried out pickling after, be cold-rolled to the thickness of slab shown in the table 6, carry out final annealing at 980 ℃.Along these cold rolled annealed plate rolling direction, become 45 ° direction with rolling direction, become 90 ° direction to cut JIS13 B test film with rolling direction, each test film is given 15% tension strain after, try to achieve average r value.Average r value is to be good more than 1.30, is lower than 1.30 for bad.
In addition; Take No. 4 test films (rolling direction be take direction, impact direction be that the width of rolling width direction, test film is a thickness of slab) of each 5 JIS Z, 2202 regulation; According to the regulation of JIS Z 2242, in test temperature: implement Charpy impact test under-50 ℃ the condition.Charpy impact value to 5 averages, with 100J/cm
2Above average evaluation is good, is lower than 100J/cm
2Average evaluation is bad.In addition, with 150J/cm
2Above average evaluation is good for extremely.
And, according to JIS G 0577,, in 3.5%NaCl solution, 30 ℃, measure pitting potential to the test film of taking from cold rolled annealed plate to obtain, estimate erosion resistance.Good with being evaluated as more than the 180mV vsSCE, be lower than 180mV vs SCE and be evaluated as bad.
With the result who obtains in the lump table 6 illustrate.As shown in table 6, cold rolling draft is that steel plate No.44 ~ 47,52 ~ 56,58 ~ 61,63 ~ 64 more than 65%, 66 ~ 74 average r value are more than 1.30, and-50 ℃ Charpy impact value is 100J/cm
2More than, toughness is high, and pitting potential is that erosion resistance is good more than the 180mV vs SCE.
On the other hand, the cold rolling draft average r value that is lower than 65% steel plate No.50 ~ 51 is lower than 1.30.In addition, 0 ℃ Charpy impact value of steel plate No.41,42,48,49,57,62,65 hot-rolled sheet all is lower than 50J/cm
2, therefore, the plate fracture might take place, so do not carry out evaluation thereafter during through continuous annealing line under applying tension force.In addition, the pitting potential of the poor steel plate No.43 of Nb and the poor steel plate No.75 of Cr is lower than 180mV vs SCE, and erosion resistance is bad.In addition, the solubility product of Ti * N is big, the thickness of slab of hot-rolled steel sheet is 5mm and be the steel plate No.77 that 20% method of manufacture obtains based on cold rolling draft, and its Charpy impact value of-50 ℃ is lower than 100J/cm
2
Utilizability in the industry
Ferrite-group stainless steel cold-rolled steel sheet provided by the invention; The blank that erosion resistance and tenacity excellent, the structure unit that is expected to the such building of loading table top (back of the truck), screen (grating), various flooring material (variety of floor material), part (clasp) as truck, building (civil engineering and construction) purposes etc. are used etc.
Perhaps; Because ferrite-group stainless steel cold-rolled steel sheet provided by the invention is except processibility; H.T. and erosion resistance are also all excellent, so be expected to as pull and stretch purposes such as galley equipment and the blank used etc. at the structural member of the such building of various flooring materials such as the handling equipments such as loading table top of family's electrification product, truck, screen, part, construction applications etc.
Table 2
Table 3
Table 5
Table 6
Claims (8)
1. ferrite-group stainless steel cold-rolled steel sheet; In quality %, below the C:0.020%, below the Si:1.0%, below the Mn:1.0%, below the P:0.06%, below the S:0.01%, Cr:18.0 ~ 24.0%, below the Mo:0.3%, below the Ti:0.015%, below the N:0.020%, and Al:0.20 ~ 0.40%; And 10 * (C+N)≤Nb≤0.40%; And component content satisfies following formula (A), and remainder is made up of Fe and unavoidable impurities;
Ti×N≤8.0×10
-5....（A）
Wherein, each symbol of element is represented the component content in the steel, and unit is quality %.
2. ferrite-group stainless steel cold-rolled steel sheet according to claim 1 in quality %, contains below the Si:0.5%, below the Mn:0.8%, below the Ti:0.010%.
3. ferrite-group stainless steel cold-rolled steel sheet according to claim 1 in quality %, contains below the C:0.015%, below the N:0.015%.
4. according to each described ferrite-group stainless steel cold-rolled steel sheet in the claim 1 ~ 3,, also contain at least one among following group of A and the group B in quality %,
Group A: be selected from below Cu:0.3 ~ 0.8%, Ni:1.0% and in below the Co:1.0% more than a kind;
Group B:B:0.0002 ~ 0.0020%.
5. according to each described ferrite-group stainless steel cold-rolled steel sheet in the claim 1 ~ 4, the Charpy impact value the when summer behind the final annealing of said cold-rolled steel sheet, ratio impacted characteristic in-50 ℃ is 100J/cm
2More than.
6. the method for manufacture of a ferrite-group stainless steel cold-rolled steel sheet; Be that the steel billet of each described composition heats in the claim 1 ~ 4 to having, hot rolling, hot-rolled steel sheet annealing, pickling, cold rolling, final annealing and make the method for ferrite-group stainless steel cold-rolled steel sheet; Wherein, with after the said hot rolling and the thickness of the hot-rolled steel sheet before the hot-rolled steel sheet annealing process more than the 6mm.
7. the method for manufacture of ferrite-group stainless steel cold-rolled steel sheet according to claim 6,
Charpy impact value when the summer of said hot-rolled steel sheet, ratio impacted characteristic in 0 ℃ is 50J/cm
2More than.
8. according to the method for manufacture of claim 6 or 7 described ferrite-group stainless steel cold-rolled steel sheets, said rolling draft when cold rolling is made as more than 30%.
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| JP5793459B2 (en) | 2012-03-30 | 2015-10-14 | 新日鐵住金ステンレス株式会社 | Heat-resistant ferritic stainless steel cold-rolled steel sheet excellent in workability, ferritic stainless hot-rolled steel sheet for cold-rolled material, and production method thereof |
| UA111115C2 (en) | 2012-04-02 | 2016-03-25 | Ейкей Стіл Пропертіс, Інк. | cost effective ferritic stainless steel |
| MX2015013765A (en) | 2013-03-27 | 2016-02-26 | Nippon Steel & Sumikin Sst | Hot-rolled ferritic stainless-steel plate, process for producing same, and steel strip. |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111850421A (en) * | 2016-07-04 | 2020-10-30 | 新日铁住金不锈钢株式会社 | Ferritic stainless steel sheet and method for producing ferritic stainless steel material |
| CN111850421B (en) * | 2016-07-04 | 2022-05-24 | 新日铁住金不锈钢株式会社 | Ferritic stainless steel sheet and method for producing ferritic stainless steel material |
| CN106435103A (en) * | 2016-10-13 | 2017-02-22 | 江苏金坛绿能新能源科技有限公司 | Technological method for improving corrosion resistance of ferritic stainless steel |
| CN106399833A (en) * | 2016-11-28 | 2017-02-15 | 东北大学 | Medium-chromium molybdenum-free ferritic stainless steel extremely low in brittle transition temperature and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4831257B2 (en) | 2011-12-07 |
| KR20120099520A (en) | 2012-09-10 |
| KR101463525B1 (en) | 2014-11-19 |
| CN102741445B (en) | 2014-12-17 |
| JP2011179116A (en) | 2011-09-15 |
| TW201137132A (en) | 2011-11-01 |
| TWI428454B (en) | 2014-03-01 |
| WO2011096454A1 (en) | 2011-08-11 |
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