CN105506499A - Ferrite stainless steel with good bending appearance and manufacturing method thereof - Google Patents
Ferrite stainless steel with good bending appearance and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a ferrite stainless steel with good bending appearance and a manufacturing method thereof. The ferrite stainless steel comprises the following chemical components by weight: less than or equal to 0.015% of C, less than or equal to 0.020% of N, less than or equal to 1.0% of Si, less than or equal to 1.0% of Mn, less than or equal to 0.030% of P, less than or equal to 0.010% of S, 18-22% of Cr, 0.30-0.50% of Cu, less than or equal to 0.30% of Ni, 0.3-0.6% of Nb, 0.005-0.06% of Al, 0.0010-0.005% of Ca, greater than or equal to 10(C+N) of Nb, and the balance Fe and inevitable impurities. According to the invention, Nb stabilization and a reasonable heat treatment process are employed to maximumly control the ferrite grain size so as to obtain a satisfactory appearance. At the same time, the stainless steel has good corrosion resistance and processing properties, and does not contain precious alloy elements, thus having good application prospects.
Description
Technical field
The present invention relates to a kind of ferritic stainless steel and the manufacture method thereof with good bending outward appearance, be applicable to make conduplication side appearance requirement very high elevator, household electrical appliances etc.
Background technology
Ferritic stainless steel, the ferritic stainless steel that special carbon containing, nitrogen are very low has excellent solidity to corrosion, plasticity and weldability, and there is high product cost and beautiful outward appearance, be that World Key develops and substitutes the resource-conserving product of austenitic stainless steel, the field such as elevator, household electrical appliances can be widely used in.But to when requiring the purposes of bending and forming, existing ferritic stainless steel bending outward appearance is in most of the cases also unsatisfactory, the principal element affecting bending outward appearance is the surperficial orange peel phenomenon after bending.
In prior art, as follows to the Patents of the ferritic stainless steel improving bending outward appearance:
The disclosed a kind of ferritic stainless steel of Japanese Patent JP2008274330 (A), its composition by weight percent is: C≤0.01%, Si:0.03 ~ 0.6%, Mn:0.1 ~ 0.5%, P≤0.05%, S≤0.01%, Cr:20 ~ 25%, Ti:0.5 ~ 1.0%, B:0.0005 ~ 0.003%, N:0.015 ~ 0.03%.
A kind of ferritic stainless steel disclosed in Chinese patent CN98801478.5, its composition by weight percent is: C:0.001 ~ 0.015%, Si≤1.0%, Mn≤1.0%, P≤0.05%, S≤0.010%, Cr:8 ~ 30%, Al≤0.08%, N:0.005 ~ 0.015%, O≤0.0080%, Ti≤0.25%, Ti/N >=12, Nb and V content meets (Nb+V): 0.05 ~ 0.10%, and V/Nb:2 ~ 5.
A kind of ferritic stainless steel disclosed in Japanese Patent JP10017999, its composition by weight percent is: C≤0.02%, N≤0.02%, Si≤2.0%, Mn≤0.8%, Cr:10 ~ 25.0%, Ni≤1.0%, (Ti/48+Nb/93)/(C/12+N/14) >1.5 (Ti+Nb) <0.5%.
A kind of ferritic stainless steel disclosed in Japanese Patent JP1986051012, its composition by weight percent is: C≤0.02%, Si≤1.0%, Mn≤1.0%, Cr:12 ~ 25.0%, Cu:0.10 ~ 2.0%, Nb:0.2 ~ 2.0%.
Above-mentioned patent concentrates on deep-draw and surface in deep-draw process and resists the research of wrinkling performance.For improving the plasticity of ferritic stainless steel and anti-wrinkling performance, usual employing Nb, Ti bistable or the mono-Stabilization of Ti, by improve strand equiaxial crystal ratio, improve single pass roughing and finish rolling draft, reduce finishing temperature and coiling temperature, increase hot rolled coil recrystallization annealing number of times, increase cold rolling draft, the measure such as cold rolled annealed, obtain favourable texture to improve plasticity.
Chinese patent CN98801478.5 discloses " deep drawing quality and the good ferritic stainless steel of resistance to ridging and manufacture method " thereof, this patent mainly by adding Nb, Ti stabilizing element in ferritic stainless steel, promote the precipitation of TiN, and control by the product proportioning that Ti and N is certain, and TiN promotes the formation of equiax crystal as the forming core particle in liquid phase, and then improve final texture, improve plasticity.
But the steel grade involved by above-mentioned patent, relating generally to the wrinkling process of shaping improving ferritic stainless steel after punching press, is not the process for the ferritic stainless steel with good bending outward appearance.
Summary of the invention
The object of the present invention is to provide a kind of ferritic stainless steel and the manufacture method thereof with good bending outward appearance, this ferritic stainless steel obtains satisfied bending outward appearance, grain-size≤20 μm in gained finished product ferritic stainless steel by controlling ferrite grain size to greatest extent with Nb stabilization and optimum treatment process.Meanwhile, because this stainless steel has good solidity to corrosion, and not containing expensive alloying elements, cost is low.
For achieving the above object, technical scheme of the present invention is:
By adding Nb stabilizing element and adopt rational hot-roll annealing temperature and cold rolled annealed temperature, the remarkable refinement grain-size of ferritic stainless steel; Improve ferritic resistance to pitting attack performance.Resistance to pitting attack performance and atmospheric corrosion resistance reach the level of 304.By Ca process, brittle inclusion changes into the moulding inclusion of low melting point.Flanging cracking is avoided.
Particularly, a kind of ferritic stainless steel with good bending outward appearance of the present invention, its chemical component weight per-cent is: C≤0.015%, N≤0.020%, Si:0.1 ~ 1.0%, Mn:0.1 ~ 1.0%, P≤0.030%, S≤0.010%, Cr:18 ~ 22%, Cu:0.30 ~ 0.50%, Ni≤0.30%, Nb:0.3 ~ 0.6%, Al:0.005 ~ 0.06%, Ca:0.0010 ~ 0.005%, Nb >=10 (C+N), all the other are Fe and inevitable impurity.
Further, grain-size≤20 μm of described ferritic stainless steel.
Have in the Composition Design of the ferritic stainless steel of good bending outward appearance in the present invention:
The key improving ferritic stainless steel bending surface orange peel phenomenon is crystal grain thinning.When crystal grain is enough tiny, the local deformaton that bending causes will be evenly distributed among more crystal grain, and the distortion of each crystal grain reduces relatively, and intercrystalline relative slippage reduces, and the surface of bending part is more level and smooth.Generally speaking, when ferritic stainless steel grain-size is more than 50 μm, will produce orange peel phenomenon in post-production process, general acceptable grain-size is about 30 μm, but this application very harsh to appearance requirement for elevator or household electrical appliances etc., still makes us being satisfied with not.Therefore further refining grain size is necessary.
But general ferritic stainless steel is when cold rolled annealed process, and Grain growth trend is comparatively large, grows up very soon after ferrite crystal grain recrystallize.For Ti stabilization ferritic stainless steel, TiN precipitate size is 3-5um, and to grain growth without contribution, and tiny precipitated phase TiC dissolves under higher annealing temperature, can not stop grain growth.On the contrary, Nb can be used for fining ferrite grains effectively, and this is attributable to the pinning effect of Nb (CN) and solid solution Nb atom pairs crystal boundary.Except Grain refinement, Nb also has many-sided beneficial effect in ferritic stainless steel, carbon in steel, nitrogen interstitial atom can be combined and forms stable carboritride, inhibit Cr23C6 in the precipitation of crystal boundary, thus improve solidity to corrosion; Nb is at high temperature solid-solution in ferrite matrix, by solution strengthening, can effectively improve ferritic stainless steel hot strength.The present invention makes full use of these beneficial effects of Nb element, has invented the ferritic stainless steel with good buckling performance.
In addition, the inclusion conduplication side outward appearance of aluminium also has material impact.Larger inclusion not only causes steel surface imperfection, and will cause flanging place fine crack.Therefore, when VOD vacuum metling, long-time argon gas stir process should be adopted, make inclusion floating in slag, to reduce inclusion content; When continuous casting, the prerequisite of inclusion floating should be created, be strictly on guard against secondary oxidation; Adopt inclusions class, make inclusion become the moulding of low melting point from brittle inclusion and be mingled with.
Cr:Cr is topmost alloying element in stainless steel, along with the increase of Cr content, stainless steel in oxidizing acid media solidity to corrosion, at Cl
-in solution, anticorrosion stress-resistant, spot corrosion, crevice corrosion ability are significantly increased.By ensure exploitation ferritic stainless steel there is good corrosion resistance nature, in the present invention, the Cr content of ferritic stainless steel is limited in 18 ~ 22wt%.
Cu:Cu can improve stainless steel erosion resistance, significantly improves the cold forming capability of ferritic stainless steel, but too much Cu easily separates out with ε-Cu when annealing, and causes the decline of cold-forming property and corrosion resistance nature.Therefore, Cu content is limited in 0.3 ~ 0.5wt%.
Nb:Nb and C, N have very strong chemosynthesis, on the one hand, by forming stable Nb (CN) compound, prevent the C compound owing to forming Cr and corrosion proof decline that the Cr concentration that causes reduces and causes, on the other hand, Nb by being solid-solubilized in ferrite matrix, by hindering the fast growth of ferrite crystal grain in annealing process, strong fining ferrite grains, thus reduce the orange peel phenomenon in Forging Process.Too high Nb, by causing the precipitation of Laves phase Fe2Nb, causes penalty.Usually, C in fixing steel, minimized content needed for atom N should meet: Nb >=10 (C+N).Determine Nb:0.3 ~ 0.6wt% thus.
C:C is harmful element in ferritic stainless steel.Because in alloy, Cr content is very high, and in ferrite, the solubleness of C, than much lower in austenite, thus easily separates out M23C6 on crystal boundary.As higher than more than 800 DEG C precipitations, formed at crystal boundary mainly with particulate state, little on fragility impact; As 600 ~ 700 DEG C time, then many on crystal boundary with netted precipitation, alloy is become fragile.M23C6 is very fast with netted speed of separating out on crystal boundary, not only makes alloy become fragile, and causes serious grain boundary corrosion because of the poor Cr of crystal boundary.Therefore, for improving intergranular corrosion resistance performance and the toughness of ferritic stainless steel, must C content be reduced by smelting or adopt strong C, N compound formation element to be fixed.Owing to can not completely C be removed, according to existing smelting equipment level, regulation C≤0.015wt%.
N:N is as harmful interstitial element, and the solubleness in ferrite is also very low, when alloy Cr content is higher, easily generates Cr2N and reduces corrosion resistance nature and the toughness of ferritic stainless steel, therefore, must remove by smelting as far as possible.Owing to can not completely N be removed, according to existing smelting equipment level, regulation N≤0.020wt%.
Si:Si can be used as reductor, reductive agent in stainless steel, can effectively improve stainless high-temperature oxidation resistance, and the inclusion formed is plasticity Silicate Inclusions, less to the disadvantageous effect of polishing performance.But too much Si can cause the plasticity of steel to decline.Regulation Si≤1.0wt%.
Mn:Mn is for expanding austenitic area element, and Mn excessive in ferritic stainless steel can cause duplex structure and make poor processability.Regulation Mn≤1.0wt%.
P, S:P, S are impurity element in steel, reduce the high-temp plastic of steel, in ferritic stainless steel hot procedure, easily and other factors one defect such as work and cause that limit is split.In addition, S also can reduce the pitting resistance of ferritic stainless steel.Therefore, its content should be reduced as far as possible.
Al: aluminium is kind of a strong reductor. when in steel, Al content reaches 0.005wt%, desoxydatoin can be played, but when aluminium too high levels, easily occur that alumina inclusion causes mold gap to block and the surperficial squama of the finished product rolls over defect, therefore specify that Al content is between 0.005 ~ 0.06wt%.
Ca: when Ca content is more than 0.0010wt% in steel, effectively can make the sex change of magnesium-aluminium spinel class brittle inclusion, form moulding being mingled with, improve surface finish performance.But when Ca content is more than 0.0050wt%, the calcic inclusion formed will reduce the corrosion resistance nature of ferritic stainless steel.Therefore, the content of calcium is 0.0010 ~ 0.0050wt%.
A kind of manufacture method with the ferritic stainless steel of good bending outward appearance of the present invention, comprises the steps:
1) smelt, cast
Ferritic stainless steel, its chemical component weight per-cent is: C≤0.015%, N≤0.020%, Si≤1.0%, Mn≤1.0%, P≤0.030%, S≤0.010%, Cr:18 ~ 22%, Cu:0.30 ~ 0.50%, Ni≤0.30%, Nb:0.3 ~ 0.6%, Al:0.005 ~ 0.06%, Ca:0.0010 ~ 0.005%, Nb >=10 (C+N), all the other are Fe and inevitable impurity; Undertaken smelting and pouring molten steel being become strand by mentioned component;
2) hot rolling, to batch
Carry out roughing after strand being heated to 1100 ~ 1180 DEG C, complete finish rolling at 750 ~ 850 DEG C, batch at 600 ~ 650 DEG C, obtain coil of strip;
3) uncoiling, annealing, pickling
Steel band is obtained, annealing temperature 950 ~ 1000 DEG C, every mm of thickness strip anneal soaking time 1 ~ 3min after the uncoiling of gained coil of strip;
4) cold rolling
Cold roling reduction 75% ~ 80%;
5) recrystallization annealing
Annealing temperature 950 ~ 1000 DEG C, every mm of thickness strip anneal soaking time 1 ~ 3min, ferrite grain size≤20 μm, obtain the ferritic stainless steel that finished product has good bending outward appearance.
Further, step 3) in, steel band is travelling speed 25 ~ 40m/min in annealing furnace.
Separately, gained finished product has grain-size≤20 μm of the ferritic stainless steel of good bending outward appearance.The pitting potential that gained finished product has the ferritic stainless steel of good bending outward appearance is 320 ~ 370mv.
Beneficial effect of the present invention is:
A) by adding Nb stabilizing element and adopting rational hot-roll annealing temperature and cold rolled annealed temperature, the remarkable refinement grain-size of ferritic stainless steel, average grain size≤20 μm;
B) refinement of ferrite stainless crystalline grain of steel significantly improves bending outward appearance;
C) by adding Nb stabilizing element, ferritic resistance to pitting attack performance is improved.Resistance to pitting attack performance and atmospheric corrosion resistance reach the level of 304;
D) by Ca process, brittle inclusion changes into the moulding inclusion of low melting point.Flanging cracking is avoided.
Accompanying drawing explanation
Fig. 1 be the embodiment of the present invention 1 steel grade grain orientation figure and
oDF sectional view.
Fig. 2 be comparative example 2 steel grade grain orientation figure and
oDF sectional view.
Fig. 3 is the steel grade grain structure figure that the embodiment of the present invention 1 steel grade obtains for scale with 200 μm.
Fig. 4 is the steel grade grain structure figure that comparative example 2 steel grade obtains for scale with 100 μm.
Fig. 5 is the embodiment of the present invention 1 steel grade bending appearance effect figure.
Fig. 6 is comparative example 2 steel grade bending appearance effect figure.
Fig. 7 is the embodiment of the present invention 1 steel grade ferrite grain size distribution plan.
Fig. 8 is comparative example 2 steel grade ferrite grain size distribution plan.
Fig. 9 is the embodiment of the present invention 1 steel grade 18 cycle accelerated corrosion photos.
Figure 10 is comparative example 2 steel grade 18 cycle accelerated corrosion photos.
Figure 11 is 304 steel, 18 cycle accelerated corrosion photos.
Embodiment
Below in conjunction with embodiment and accompanying drawing, the present invention will be further described.
The embodiment of the present invention there is the ferritic stainless steel of good bending outward appearance and comparative example steel grade chemical composition as shown in table 1, all the other are Fe and inevitable impurity.The embodiment of the present invention contrasts as shown in table 2 with comparative example key process parameter.
Table 1. embodiment of the present invention and comparative example steel grade chemical composition (unit: wt%)
| C | Si | Mn | P | S | Cr | Cu | Nb | Ti | Al | Ca | N | |
| Embodiment 1 | 0.0079 | 0.32 | 0.25 | 0.031 | 0.001 | 18.2 | 0.36 | 0.35 | - | 0.005 | 0.0012 | 0.0013 |
| Embodiment 2 | 0.0089 | 0.45 | 0.16 | 0.038 | 0.002 | 19.5 | 0.38 | 0.41 | - | 0.006 | 0.0013 | 0.0015 |
| Embodiment 3 | 0.0098 | 0.32 | 0.30 | 0.032 | 0.001 | 19.8 | 0.37 | 0.42 | - | 0.007 | 0.0021 | 0.0026 |
| Embodiment 4 | 0.014 | 0.37 | 0.22 | 0.029 | 0.002 | 20.8 | 0.40 | 0.31 | - | 0.015 | 0.0017 | 0.014 |
| Embodiment 5 | 0.0082 | 0.33 | 0.19 | 0.025 | 0.001 | 21.9 | 0.39 | 0.39 | - | 0.013 | 0.0016 | 0.0013 |
| Comparative example 1 | 0.013 | 0.20 | 0.21 | 0.033 | 0.001 | 20.4 | 0.38 | 0.22 | -- | 0.003 | -- | 0.015 |
| Comparative example 2 | 0.010 | 0.18 | 0.18 | 0.028 | 0.001 | 20.7 | 0.39 | 0.22 | 0.14 | 0.005 | -- | 0.014 |
Table 2. embodiment of the present invention contrasts with comparative example key process parameter
For improving embodiment 1 for the stainless bending effect of obtained finished iron ferritic, select three kinds of different cold rolling reductions 60%, 70% and 80% and three cold move back temperature 920 DEG C, 950 DEG C and 980 DEG C, research cold rolling reduction on cold impact of moving back recrystallize situation and bending effect.
Adopt identical cold when moving back temperature 920 DEG C, deflection 60%, 70% sample there occurs a small amount of recrystallize, and the overwhelming majority is ribbon tissue, and 80% deflection sample perfect recrystallization; After annealing temperature is elevated to 950 DEG C and 980 DEG C, can both there is recrystallize in three kinds of cold rolling reductions 60%, 70% and 80%, but 60% cold rolling reduction sample grain-size be obviously greater than after both.
When bending experimental result shows that cold rolling reduction is 80%, grain-size is minimum, and after bending, orange peel is the slightest.The reason that grain size has material impact to bending effect is as follows: when carrying out flanging distortion, each intercrystalline compatible deformation, deflection is assigned on each crystal grain of bending part, under the tiny situation of crystal grain, the deformation quantity that unit die bears diminishes, and single crystal grain Dislocations sliding deformation amount reduces, and roughness reduces, the local naked eyes of such flanging are looked and are seemed finer and closely woven, and orange peel is slighter.
On the contrary, if coarse grains, then flanging place can seem more coarse.Above-mentioned test-results describes, and adopts larger cold rolling reduction, obtains tiny ferrite crystal grain, contributes to improving product bending and resists wrinkling and anti-coarse performance, and when cold rolling reduction is 80%, bending appearance effect is best.
Table 3 is the mechanical property of the embodiment of the present invention and comparative example, the r value characterizing forming property and corresponding ferrite grain size.The visible mechanical property of the two, the r value of sign forming property there is no too big difference, but grain-size is obviously different, and embodiment crystal grain is more tiny.This is attributable to the effect of the higher Nb content of embodiment, the niobium of i.e. solid solution state and the second phase particles of niobium are easily at crystal boundary, and segregation on subgrain boundary and dislocation line, stops the motion of crystal boundary, subgrain boundary and dislocation effectively, carry out with having delayed recrystallization process, thus prevent growing up of crystal grain.Within the scope of the present invention, Nb content is higher, and this refining effect is more remarkable.
The mechanical property of table 3 embodiment of the present invention and comparative example and average grain size contrast
Fig. 1 be the embodiment of the present invention 1 steel grade grain orientation figure and
oDF sectional view.As seen from Figure 1, the texture of embodiment 1 is essentially, and { 111} γ texture, the similar continuous river of its grain orientation thread shape show that in steel grade, grain orientation is uniformly distributed along γ line, occur concentrating situation.The γ texture of different orientation is conducive to the anisotropic reducing steel, and intensity is more or less the same, and is more conducive to compatible deformation, and the outward appearance namely after steel grade bending is better.
Fig. 2 be comparative example 2 steel grade of the present invention grain orientation figure and
oDF sectional view.As seen from Figure 2, comparative example 2 steel grade has stronger { 111}<112> γ texture, the similar independently hills one by one of its grain orientation thread shape, show that in steel grade, grain orientation is crossed as concentrating, cause anisotropic stronger, also there is the α texture of a small amount of ratio, and α texture to steel grade bending and forming and wrinkling performance unfavorable.Therefore, the embodiment of the present invention has better forming property and anti-wrinkling performance.
Fig. 3 is the steel grade grain structure figure that the embodiment of the present invention 1 steel grade obtains for scale with 200 μm.Fig. 4 is the steel grade grain structure figure that comparative example 2 steel grade obtains for scale with 100 μm.Contrast known through Fig. 3, Fig. 4, under equal scale size, the embodiment of the present invention 1 steel grade grain-size is obviously than the refinement more of comparative example 2 steel grade grain-size.
The embodiment of the present invention 1 steel grade bending appearance effect as shown in Figure 5.Comparative example 2 steel grade bending appearance effect as shown in Figure 6.Two steel grades all carry out Bending Processing by elevator plate complete processing, can find out, the whitened area, bending part of comparative example 2 steel grade is wider and bending part is comparatively coarse; And the bending part of the embodiment of the present invention 1 steel grade is level and smooth, fine and smooth, appearance effect is much better than comparative example 2.
Ferrite grain size directly has influence on bending outward appearance.When grain-size is 35-60um, orange peel is serious, unacceptable; When grain-size is 20 ~ 35um, orange peel is comparatively light, can accept; Grain-size is for being less than 20um, and orange peel is very light, and bending outward appearance is good.
Fig. 7 is the embodiment of the present invention 1 steel grade ferrite grain size distribution plan.Fig. 8 is comparative example 2 steel grade ferrite grain size distribution plan.Known through contrasting, the embodiment of the present invention 1 steel grade ferrite grain size concentrates on the region being less than or equal to 20 μm mostly, and average grain size is 16 μm.The region of > 20 μm and comparative example 2 steel grade ferrite grain size focuses mostly on greatly, average grain size is 29 μm, and this flanging outward appearance that directly results in the embodiment of the present invention 1 steel grade is obviously better than comparative example 2 steel grade.
Table 4 is the pitting potential contrast of the embodiment of the present invention and comparative example.As shown in Table 4, the pitting potential of the embodiment of the present invention and comparative example steel grade all reaches 304 stainless levels, but the pitting potential measuring higher embodiment of the present invention steel grade containing Nb measures low comparative example steel grade apparently higher than containing Nb.This is attributable to the effect of Nb equally.On the one hand, Nb and C, N combine, and form Nb (CN), inhibit the precipitation of M23C6 phase, avoid the poor Cr of crystal boundary.On the other hand, improve along with containing Nb amount, the solid solution Nb content in ferrite matrix increases, and causes the further segregation of grain boundaries Nb atom, and then result in the enrichment of Cr at crystal boundary.These two aspects factor result in embodiment of the present invention steel grade and has higher pitting potential.
The pitting potential contrast of table 4. embodiment of the present invention and comparative example
| Measure current potential | Measure current potential | Measure current potential | Average potential (mv) | |
| Embodiment 1 | 352 | 360 | 371 | 361 |
| Embodiment 2 | 356 | 352 | 368 | 358 |
| Embodiment 3 | 346 | 353 | 366 | 355 |
| Embodiment 4 | 341 | 361 | 345 | 349 |
| Embodiment 5 | 347 | 351 | 352 | 350 |
| Comparative example 1 | 353 | 345 | 351 | 349 |
| Comparative example 2 | 330 | 340 | 320 | 345 |
| 304 steel | 336 | 342 | 359 | 345 |
In addition, accelerated corrosion test can contrast corrosion proof difference preferably.
Specimen surface #600 sand paper carries out polishing, and the test period is 30, and each cycle divides three steps to carry out, that is, spray salt (5%NaCl, 35 DEG C, 2 hours) → dry (60 DEG C, 4 hours) → wet (40 DEG C, 2 hours).
Fig. 9 is the embodiment of the present invention 1 steel grade 18 cycle accelerated corrosion photos.Figure 10 is comparative example 2 steel grade 18 cycle accelerated corrosion photos.Figure 11 is 304 steel grade, 18 cycle accelerated corrosion photos.In Fig. 9, after 18 the cycles acceleration corruption of the embodiment of the present invention 1 steel grade, smooth surface, as minute surface, can be formed as mirror reflection effect on surface.And after comparative example 2 steel grade and 304 steel grades, 18 cycles accelerate corruption, surface is obviously dirty, there is no reflecting effect.The solidity to corrosion of the visible embodiment of the present invention 1 steel grade is better than comparative example 2 and 304 steel grade.
As mentioned above, adopt the high Cr ferritic stainless steel that the present invention can provide a kind of bending outward appearance good, this ferritic stainless steel has the corrosion resistance nature suitable with 304 stainless steels, has broad application prospects at elevator and household electric appliances.
It should be noted that, above embodiment is only in order to illustrate technical scheme of the present invention and unrestricted.Although with reference to preferred embodiment to invention has been detailed description, those of ordinary skill in the art is to be understood that, can modify to the technical scheme of invention or equivalent replacement, and not depart from the scope of technical solution of the present invention, it all should be encompassed in right of the present invention.
Claims (6)
1. have a ferritic stainless steel for good bending outward appearance, its chemical component weight per-cent is: C≤0.015%, N≤0.020%, Si:0.1 ~ 1.0%, Mn:0.1 ~ 1.0%, P≤0.030%, S≤0.010%, Cr:18 ~ 22%, Cu:0.30 ~ 0.50%, Ni≤0.30%, Nb:0.3 ~ 0.6%, Al:0.005 ~ 0.06%, Ca:0.0010 ~ 0.005%, Nb >=10 (C+N), all the other are Fe and inevitable impurity.
2. the ferritic stainless steel with good bending outward appearance according to claim 1, is characterized in that, grain-size≤20 μm of described ferritic stainless steel.
3. there is a manufacture method for the ferritic stainless steel of good bending outward appearance, comprise the steps:
1) smelt, cast
Ferritic stainless steel, its chemical component weight per-cent is: C≤0.015%, N≤0.020%, Si:0.1 ~ 1.0%, Mn:0.1 ~ 1.0%, P≤0.030%, S≤0.010%, Cr:18 ~ 22%, Cu:0.30 ~ 0.50%, Ni≤0.30%, Nb:0.3 ~ 0.6%, Al:0.005 ~ 0.06%, Ca:0.0010 ~ 0.005%, Nb >=10 (C+N), all the other are Fe and inevitable impurity; Undertaken smelting and being cast into strand by mentioned component;
2) hot rolling, to batch
Carry out roughing after strand being heated to 1100 ~ 1180 DEG C, complete finish rolling at 750 ~ 850 DEG C, batch at 600 ~ 650 DEG C, obtain coil of strip;
3) uncoiling, annealing, pickling
Steel band is obtained, annealing temperature 950 ~ 1000 DEG C, every mm of thickness strip anneal soaking time 1 ~ 3min after the uncoiling of gained coil of strip;
4) cold rolling
Cold roling reduction 75% ~ 80%;
5) recrystallization annealing
Annealing temperature 950 ~ 1000 DEG C, every mm of thickness strip anneal soaking time 1 ~ 3min, ferrite grain size≤20 μm, obtain the ferritic stainless steel that finished product has good bending outward appearance.
4. manufacture method according to claim 3, is characterized in that, step 3) in, described steel band is travelling speed 25 ~ 40m/min in annealing furnace.
5. manufacture method according to claim 3, is characterized in that, gained finished product has grain-size≤20 μm of the ferritic stainless steel of good bending outward appearance.
6. manufacture method according to claim 3, is characterized in that, the pitting potential that gained finished product has the ferritic stainless steel of good bending outward appearance is 320 ~ 370mv.
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| CN110684926A (en) * | 2019-10-21 | 2020-01-14 | 宁波宝新不锈钢有限公司 | Ferritic stainless steel and preparation method thereof |
| CN112501513A (en) * | 2020-11-30 | 2021-03-16 | 日照宝华新材料有限公司 | Low-carbon acid-pickled steel with excellent formability and surface quality and production method thereof |
| CN113767181A (en) * | 2019-05-29 | 2021-12-07 | 杰富意钢铁株式会社 | Ferritic stainless steel sheet and method for producing same |
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| JPH0630831B2 (en) * | 1984-11-17 | 1994-04-27 | 新日本製鐵株式会社 | Pressure vessel with excellent corrosion resistance and hydrogen delamination cracking resistance |
| CN101899625A (en) * | 2009-05-25 | 2010-12-01 | 宝山钢铁股份有限公司 | Ferrite stainless steel and manufacturing method thereof |
| CN103510013A (en) * | 2013-09-29 | 2014-01-15 | 宝钢不锈钢有限公司 | Tin-containing ferritic stainless steel with good wrinkle resistance and manufacturing method thereof |
| CN103741053A (en) * | 2013-12-26 | 2014-04-23 | 宝钢不锈钢有限公司 | Ferrite stainless steel with good polishing performance and manufacturing method thereof |
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| CN113767181A (en) * | 2019-05-29 | 2021-12-07 | 杰富意钢铁株式会社 | Ferritic stainless steel sheet and method for producing same |
| CN110684926A (en) * | 2019-10-21 | 2020-01-14 | 宁波宝新不锈钢有限公司 | Ferritic stainless steel and preparation method thereof |
| CN112501513A (en) * | 2020-11-30 | 2021-03-16 | 日照宝华新材料有限公司 | Low-carbon acid-pickled steel with excellent formability and surface quality and production method thereof |
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