CN102725432A - Highly corrosion-resistant hot-rolled ferrite stainless steel sheet having excellent toughness - Google Patents
Highly corrosion-resistant hot-rolled ferrite stainless steel sheet having excellent toughness Download PDFInfo
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- CN102725432A CN102725432A CN2011800072108A CN201180007210A CN102725432A CN 102725432 A CN102725432 A CN 102725432A CN 2011800072108 A CN2011800072108 A CN 2011800072108A CN 201180007210 A CN201180007210 A CN 201180007210A CN 102725432 A CN102725432 A CN 102725432A
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/06—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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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Abstract
Disclosed is a highly corrosion-resistant hot-rolled ferrite stainless steel sheet having excellent toughness, which has a Charpy impact value of 100 J/cm2 or more at -50 DEG C. Specifically disclosed is a hot-rolled ferrite stainless steel sheet 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, 0.15-0.40% of Nb, 0.015% or less of Ti, 0.020% or less of N and 0.20-0.40% of Al, wherein these components fulfill the requirements represented by formulae (A) and (B) and Fe and unavoidable impurities make up the remainder. TiN <= 8.0x10-5(A) 10x(C+N) <= Nb <= 0.25+(C/12+N/14)x93 (B) (In the formulae, each element symbol represents the content (expressed in mass%) of the element in the steel.
Description
Technical field
The present invention relates to the excellent high corrosion resistance ferrite-group stainless steel hot-rolled steel sheet (high-corrosion resistance hot rolled ferritic stainless steel sheet) of toughness (toughness).
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.Not containing in a large number in the ferrite-group stainless steel of Ni,, 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).SUS430J1L (19%Cr-0.5%Cu-0.4%Nb) (JIS G 4305) is arranged, but also it has enough toughness hardly as structure unit in the ferrite-group stainless steel that does not contain Mo.
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 ferrite series stainless steel plate of the tenacity excellent of structure unit purposes.In addition, in order in the structure unit purposes, stably to use, the thickness of slab of preferred steel plate is more than the 5mm.
To this; As the flexible technology of improving ferrite series stainless steel plate; 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: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%, Ti * N:0.0005 is above, remainder is Fe and can not keeps away impurity, 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 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 applicable to the thicker purposes of slab.In addition, in the patent documentation 2, Ti is decentralised control (dispersion control) difficulty of inclusion, because of its thickization reduces the toughness of hot-rolled steel sheet easily, can not obtain enough toughness.Should explain, consider supposition under the situation of the building materials field that cold district (cold latitudes) uses, think that the Charpy impact value of needs-50 ℃ is 100J/cm
2Above toughness.
Patent documentation 1: TOHKEMY 2008-190035 communique
Patent documentation 2: TOHKEMY 2001-020046 communique
Summary of the invention
As previously discussed, in based on the technology that contains Mo, Ti, also fully do not realize the tough property improvement of ferrite-group stainless steel hot-rolled steel sheet.
The Charpy impact value that the object of the present invention is to provide-50 ℃ is 100J/cm
2The high corrosion resistance ferrite-group stainless steel hot-rolled steel sheet of above tenacity excellent.
Contrivers etc. are in order to solve above-mentioned problem, to like patent documentation 1, contain Nb 2, but the acquisition methods that does not contain ferrite-group stainless steel hot-rolled steel sheet Ni or Mo, erosion resistance and tenacity excellent of high price is furtherd investigate.
Below, short of special instruction, the % of chemical ingredients all representes the meaning of quality %.
At first, to realizing that experimental result of the present invention describes.Contrivers etc. are in order to estimate the flexible influence of Al to ferrite-group stainless steel; Melting the low N steel of the low C-of 21%Cr-0.25%Nb-and make the Al amount carry out the steel that changes at 0.03 ~ 0.50%; Make the hot-roll annealing plate (hot rolled and annealed steel sheet) (hot-rolled steel sheet) of thickness of slab 5mm and 6mm, under-50 ℃, carried out Charpy impact test (Charpy impact test).Its result illustrates at Fig. 1.Can know that Charpy impact value becomes 100J/cm through making Al measure the scope 0.20 ~ 0.40%
2More than, can access excellent toughness.Infer that its reason is through making Al amount more than 0.20%, reduced the O amount in the steel, reduced due to inclusion (inclusion) etc.In addition, the flexible when surpassing 0.40% scope about the Al amount reduces, and thinks because due to the increase of solid solution Al.
Then, for estimate Ti, N influences flexible, melting the low N steel of the low C-of the 21%Cr-0.25%Nb-shown in the table 1 and 2 and make the steel of Ti, N quantitative changeization, the steel of use table 1 is made the hot-roll annealing plate of thickness of slab 5mm, under-50 ℃, has carried out Charpy impact test.In addition, the steel of use table 2 is made the hot-roll annealing plate of thickness of slab 6mm, under-50 ℃, has carried out Charpy impact test.Should explain, in these experiments, the absorption that Charpy impact value (charpy impact value) expression will obtain through Charpy impact 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.
With its result shown in table 1, table 2 and Fig. 2.Can know that if be equivalent to Ti (the %) * N (%) (below be called " solubility product ") of the solubility product (solubility product constant) of Ti and N be 8.0 * 10
-5Below, then Charpy impact value is stablized and is 100J/cm
2More than, can access excellent toughness.In order to investigate this reason, be 8.0 * 10 to solubility product
-5Below and surpass 8.0 * 10
-5The section structure (sectional structure) of experiment 2-4 and the sample of experiment 2-5 of experiment 1-5 and sample and the table 2 of experiment 1-6 of table 1 grind after; With chloroazotic acid (aqua regalis) corrosion, with sem (electron scanning microscope) (SEM) and energy dispersion type X-ray analyzer (energy dispersive X-ray analyzer) (EDX) carried out observation, the analysis of precipitate.Its result is 8.0 * 10 at solubility product
-5Below and to have observed diameter in the sample of the experiment 2-4 of the experiment 1-5 of the table 1 of H.T. and table 2 be the small globular Nb carbide (carbide) of 200 ~ 300nm.On the other hand, surpass 8.0 * 10 at solubility product
-5The sample of experiment 2-5 of experiment 1-6 and table 2 of low flexible table 1 in, having observed a plurality of diameters is the Ti nitride (nitride) of 2 ~ 5 μ m thick rectangular-shaped (rectangular solid like).Think that this is because solubility product surpasses 8.0 * 10
-5The time, separate out Ti nitride and thickization from the solidification stages of molten steel, because of notch effect (notch effect) reduces toughness.
Find by above experimental result; From the viewpoint of its erosion resistance with the property made; The content of Cr is made as 18.0 ~ 24.0%; As described above the solubility product of Al amount and Ti and N is controlled, thereby can be suppressed to belong to the inclusion of the thick Al that reduces toughness solidification stages important factor, molten steel, the generation of Ti nitride, can access the high corrosion resistance ferrite-group stainless steel hot-rolled steel sheet of tenacity excellent.The present invention is based on above opinion and accomplishes.
That is of the present invention being constructed as follows.
(1) a kind of ferrite-group stainless steel hot-rolled steel sheet; It is characterized in that; In quality %; Contain 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%, Nb:0.15 ~ 0.40%, below the Ti:0.015%, below the N:0.020%, Al:0.20 ~ 0.40%, and satisfy following formula (A) and (B), remainder is made up of Fe and unavoidable impurities;
Ti×N≤8.0×10
-5...（A）
10×（C＋N）≤Nb≤0.25＋（C／12＋N／14）×93...（B）
Wherein, each symbol of element is represented the component content (quality %) in the steel.
(2) according to (1) described ferrite-group stainless steel hot-rolled steel sheet; It is characterized in that; In quality %, for below the C:0.015%, below the Si:0.5%, below the Mn:0.8%, below Nb:0.15 ~ 0.35%, Ti:0.010%, below the N:0.015%, Al:0.20 ~ 0.35%.
(3) according to (1) or (2) described ferrite-group stainless steel hot-rolled steel sheet, it is characterized in that, in quality %, also contain be selected from below Cu:0.3 ~ 0.8%, the Ni:1.0%, at least a in below the Co:1.0%.
(4) according to each described ferrite-group stainless steel hot-rolled steel sheet in (1) ~ (3), it is characterized in that,, also contain B:0.0002 ~ 0.0020% in quality %.
According to the present invention, the Charpy impact value that can access-50 ℃ is 100J/cm
2The high corrosion resistance ferrite-group stainless steel hot-rolled steel sheet of above tenacity excellent.
Description of drawings
Fig. 1 is the figure of the influence of right-50 ℃ Charpy impact value of expression Al amount.
Fig. 2 is the figure of the influence of expression Ti (%) * Charpy impact value that N (%) is right-50 ℃.
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 forms the Cr carbide easily, if surpass 0.020%, forms the Cr carbide at heat affected zone (heat-affected zone) when then welding, and becomes the reason of grain boundary corrosion (intergranular corrosion).Therefore, C is made as below 0.020%.Be preferably below 0.015%.When further requiring high corrosion resistance, more preferably be made as below 0.010%.Should explain that (refining cost) when becoming problem, preferably is made as more than 0.003% when the refining cost.
Below the Si:1.0%
If Si surpasses 1.0% then toughness is reduced.Therefore, Si is made as below 1.0%.Be preferably below 0.5%, more preferably below 0.3%.Should explain, because Si is as the useful element of reductor (deoxidizing agent), so preferably be made as more than 0.05%.
Below the Mn:1.0%
If Mn surpasses 1.0%, then form dissolvable sulfide (fusible sulfide) MnS, erosion resistance is reduced.Therefore, Mn is made as below 1.0%.Be preferably below 0.8%, more preferably below 0.6%.
Below the P:0.06%
If P surpasses 0.06%, then not only harmful to erosion resistance, also, solution strengthening (solid solution strengthening) reduces owing to making processibility (workability).Therefore, P is made as below 0.06%.If consider processibility and toughness, then be preferably below 0.04%.
Below the S:0.01%
If it is S surpasses 0.01%, then harmful to erosion resistance.Therefore, S is made as below 0.01%.Viewpoint from high corrosion resistance is 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 is lower than 18.0%, then can not obtain sufficient erosion resistance.On the other hand,, then be easy to generate σ phase embrittlement (sigma phase embrittlement) and 475 ℃ of fragility, reduce toughness easily if surpass 24.0%.Therefore, Cr is made as 18.0 ~ 24.0%.Viewpoint from high corrosion resistance is preferably 20.0 ~ 24.0%.
Below the Mo:0.3%
If Mo surpasses 0.3%, then generate Laves and equate thick intermetallic compound, reduce toughness.Therefore, Mo is made as below 0.3%.Should explain, rise, under the even more important situation of high corrosion resistance, preferably be made as more than 0.1% than cost.
Nb：0.15~0.40%
If contain the Nb more than 0.15%, thereby then has the effect of fixation of C, N inhibition sensitization.On the other hand,, then generate Laves phase thick intermetallic compounds such as (Laves phase), reduce toughness if surpass 0.40%.Therefore, Nb is made as 0.15 ~ 0.40%.If consideration toughness then is preferably 0.15 ~ 0.35%, more preferably 0.15 ~ 0.30%.
Below the Ti:0.015%
Ti forms thick nitride, reduces toughness.Therefore, Ti is made as below 0.015%.Be preferably below 0.010%.Further require more preferably to be made as below 0.005% under the situation of H.T..
Below the N:0.020%
If N surpasses 0.020%, then form nitride, reduce toughness.Particularly with the situation of Ti coexistence under, generate thick Ti nitride from the solidification stages of molten steel, significantly reduce because of its notch effect makes toughness.Therefore, N is made as below 0.020%.Be preferably below 0.015%.Further require more preferably to be made as below 0.010% under the situation of H.T..
Al：0.20~0.40%
Al is the important element among the present invention, has the flexible of raising effect.For the toughness as 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) reduces.Therefore, Al is made as 0.20 ~ 0.40%.Be preferably 0.20 ~ 0.35%.Further require more preferably to be made as 0.20 ~ 0.30% under the situation of H.T..
Ti×N≤8.0×10
-5
As stated, belong to the thick Ti nitride of the important factor that the toughness of ferrite-group stainless steel hot-rolled steel sheet reduces, generate from the solidification stages of molten steel.In order to suppress the generation of this Ti nitride, need solubility product Ti * N be defined as 8.0 * 10
-5Below.Be preferably 5.0 * 10
-5Below.Here, Ti, N represent the content of composition (quality %) separately.
10×（C＋N）≤Nb≤0.25＋（C／12＋N／14）×93
Nb have with the deleterious C of erosion resistance, N are fixed as Nb carbide, Nb nitride, they compound precipitate and make their innoxious effects that improves erosion resistance.But if Nb amount is lower than 10 times of (C+N) amount, then Nb carbide, Nb nitride, their separating out of compound precipitate become insufficient, and Cr carbide, Cr nitride, their compound precipitate are separated out, and erosion resistance descends.Therefore, Nb is defined as more than 10 * (C+N) %.Be preferably more than 12 * (C+N) %.On the other hand, contain the Nb that surpasses ［ 0.25+ (C/12+N/14) * 93 ］ %, then can increase solid solution Nb, reduce toughness.Therefore, Nb is defined as ［ 0.25+ (C/12+N/14) * 93 ］ below the %.Here, C, N, Nb represent the content of composition (quality %) separately.
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.
Should explain, if be below the C:0.015%, below the Si:0.5%, below the Mn:0.8%, Nb:0.15 ~ 0.35%, below the Ti:0.010%, below the N:0.015%, Al:0.20 ~ 0.35%, Charpy impact value then-50 ℃ is 150J/cm
2More than, more excellent toughness can be accessed, and more excellent erosion resistance can be accessed.
Ferrite-group stainless steel hot-rolled steel sheet of the present invention must obtain the purpose characteristic by element because of above-mentioned, but can also contain following element according to desirable characteristic.
Cu：0.3~0.8%
Cu is the element that is used to improve erosion resistance, particularly effective elements aspect reduction crevice corrosion (crevice corrosion).In order to bring into play this effect, be necessary for more than 0.3%.On the other hand, if surpass 0.8%, then hot workability reduces.Therefore, Cu is made as 0.3 ~ 0.8%.Be preferably 0.3 ~ 0.5%.
Below the Ni:1.0%
Ni has the effect that reduces crevice corrosion.The effect that hot workability descends when in addition, preventing to contain Cu in addition.In order to obtain this effect, Ni is preferably more than 0.05%.But,, then cause cost to increase, and its effect is saturated, reduces hot workability on the contrary if surpass 1.0%.Therefore, Ni is made as below 1.0%.Be preferably 0.05 ~ 0.4%.
Below the Co:1.0%
Co helps to improve the flexible element.In order to obtain this effect, Co is preferably more than 0.05%.But,, ductility (ductility) is reduced if surpass 1.0%.Therefore, Co is made as below 1.0%.
B：0.0002~0.0020%
B be during to pull and stretch processing (deep drawing) anti-secondary processing brittleness (resistance to cold-work embrittlement) improve effective elements.If be lower than 0.0002%, then can not obtain this effect.On the other hand, if surpass 0.0020%, then reduce hot workability and pull and stretch performance (deep drawability).Therefore, B is made as 0.0002 ~ 0.0020%.
Then, the method for manufacture to ferrite-group stainless steel hot-rolled steel sheet of the present invention describes.
The method of making ferrite-group stainless steel hot-rolled steel sheet of the present invention efficiently is, 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 surpasses 650 ℃, then batch back carbide precipitate, intermetallic compound, thereby reduce toughness, therefore preferably be made as below 650 ℃, require more preferably to be made as below 450 ℃ under the situation of H.T. more.The hot-rolled steel sheet that obtains then, carries out pickling through the scope annealing of continuous annealing at 900 ~ 1150 ℃ on pickling line.This hot-roll annealing plate can be directly as product.In addition, also can use the blank of cold rolling usefulness, implement cold rolling-final annealing and obtain cold rolled annealed plate, should cold rolled annealed plate as product.
Embodiment
His-and-hers watches 3-1 carries out melting with the ferrite-group stainless steel of the chemical ingredients shown in the table 4-1, utilizes the continuously poured legal system to get the thick steel billet of 250mm.After these steel billet was heated to 1200 ℃, roughing was thick to 35mm, make finish to gauge since 1050 ℃, 900 ℃ of end, batch with round at 500 ℃ and to cool off, obtain the hot-rolled steel sheet of thickness of slab 5mm and/or 6mm.The hot-rolled steel sheet that obtains after keeping 80 seconds (top temperature: 1100 ℃) under the condition more than 1050 ℃, is implemented naturally cooling annealing, obtain hot-roll annealing plate (hot-rolled steel sheet).
Then; According to JIS Z 2202, (width was 5mm when wherein, thickness of slab was 5mm to take each 5 No. 4 test film from the hot-roll annealing plate; Width was 6mm when thickness of slab was 6mm) (rolling direction is for taking direction; Impact direction is the rolling width direction), implement Charpy impact test in test temperature under-50 ℃ the condition, measure Charpy impact value.The Charpy impact value of 5 test films averaged obtain Charpy impact value.
In addition,,, in 30 ℃ 3.5%NaCl solution, measure pitting potential (pitting potential), if for more than the 180mV vs SCE then be judged as excellent corrosion resistance to the sample of taking from the hot-roll annealing plate to obtain according to JIS G 0577.
The result is being shown 3-2 with shown in the table 4-2.-50 ℃ Charpy impact value can knowing the hot-rolled steel sheet of being made by the steel that satisfies member condition of the present invention is 100J/cm
2More than, pitting potential is more than the 180mV vs SCE, is the high corrosion resistance ferrite-group stainless steel hot-rolled steel sheet of tenacity excellent.
Utilizability in the industry
Ferrite-group stainless steel hot-rolled steel sheet provided by the invention; Erosion resistance and tenacity excellent are so be expected to the blank of the structure unit of the building of loading table top (back of the truck), screen (grating), various flooring material (variety of floor material), part (clasp) and so on as truck, (civil engineering and construction) for building.
Claims (4)
1. ferrite-group stainless steel hot-rolled steel sheet; It is characterized in that; In quality %; Contain 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%, Nb:0.15 ~ 0.40%, below the Ti:0.015%, below the N:0.020%, Al:0.20 ~ 0.40%, and satisfy following formula (A) and (B), remainder is made up of Fe and unavoidable impurities;
Ti×N≤8.0×10
-5...（A）
10×（C＋N）≤Nb≤0.25＋（C／12＋N／14）×93...（B）
Wherein, each symbol of element is represented the component content in the steel, and unit is quality %.
2. ferrite-group stainless steel hot-rolled steel sheet according to claim 1; Wherein, In quality %, below the C:0.015%, below the Si:0.5%, below the Mn:0.8%, Nb:0.15 ~ 0.35%, below the Ti:0.010%, below the N:0.015%, Al:0.20 ~ 0.35%.
3. ferrite-group stainless steel hot-rolled steel sheet according to claim 1 and 2 wherein, in quality %, also contains and is selected from least a below Cu:0.3 ~ 0.8%, Ni:1.0% and in below the Co:1.0%.
4. according to each described ferrite-group stainless steel hot-rolled steel sheet in the claim 1 ~ 3, wherein,, also contain B:0.0002 ~ 0.0020% in quality %.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2010016100 | 2010-01-28 | ||
| JP2010-016100 | 2010-01-28 | ||
| JP2010-021080 | 2010-02-02 | ||
| JP2010021080 | 2010-02-02 | ||
| PCT/JP2011/052187 WO2011093516A1 (en) | 2010-01-28 | 2011-01-27 | Highly corrosion-resistant hot-rolled ferrite stainless steel sheet having excellent toughness |
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| CN102725432A true CN102725432A (en) | 2012-10-10 |
| CN102725432B CN102725432B (en) | 2015-04-15 |
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| KR (1) | KR101463526B1 (en) |
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| TW (1) | TWI499465B (en) |
| WO (1) | WO2011093516A1 (en) |
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| JP6071608B2 (en) | 2012-03-09 | 2017-02-01 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel plate with excellent oxidation resistance |
| 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 |
| JP5918796B2 (en) * | 2014-03-28 | 2016-05-18 | 新日鐵住金ステンレス株式会社 | Ferritic stainless hot rolled steel sheet and steel strip with excellent toughness |
| EP3708690A1 (en) * | 2016-02-02 | 2020-09-16 | Nippon Steel Stainless Steel Corporation | Cold rolled nb-containing ferritic stainless steel sheet and method for producing same |
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Also Published As
| Publication number | Publication date |
|---|---|
| KR20120099521A (en) | 2012-09-10 |
| JP4831256B2 (en) | 2011-12-07 |
| WO2011093516A1 (en) | 2011-08-04 |
| TW201143932A (en) | 2011-12-16 |
| TWI499465B (en) | 2015-09-11 |
| JP2011179114A (en) | 2011-09-15 |
| KR101463526B1 (en) | 2014-11-19 |
| CN102725432B (en) | 2015-04-15 |
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