CN105506499B - A kind of ferritic stainless steel and its manufacturing method with good bending appearance - Google Patents
A kind of ferritic stainless steel and its manufacturing method with good bending appearance Download PDFInfo
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Abstract
A kind of ferritic stainless steel and its manufacturing method with good bending appearance, chemical component weight percentage are：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), remaining is Fe and inevitable impurity.Ferritic stainless steel of the present invention controls ferrite grain size and obtains satisfied bending appearance to the maximum extent by being stabilized with Nb and rational heat treatment process；Meanwhile the stainless steel has good corrosion resistance and processing performance, and expensive alloying elements are free of, it has a good application prospect.
Description
Technical field
The present invention relates to a kind of ferritic stainless steels and its manufacturing method with good bending appearance, are suitable for making pair
The very high elevator of flanging appearance requirement, household electrical appliances etc..
Background technology
Ferritic stainless steel, the very low ferritic stainless steel of especially carbon containing, nitrogen have excellent corrosion resistance, formability and can
Weldering property, and there is high product cost and beautiful appearance, it is that World Key develops and substitutes the resource of austenitic stainless steel
Economizing type product can be widely applied to the fields such as elevator, household electrical appliances.But when purposes to requiring bending and forming, existing ferrite
Stainless steel bending appearance in most cases is simultaneously unsatisfactory, and the principal element for influencing bending appearance is the table after bending
Face orange peel phenomenon.
In the prior art, the related patents of the ferritic stainless steel to improving bending appearance are as follows：
A kind of ferritic stainless steel disclosed in Japan Patent JP2008274330 (A), composition by weight percent are：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, composition by weight percent disclosed in Chinese patent CN98801478.5 are：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 meet (Nb+V)：0.05~
0.10%, and V/Nb：2~5.
A kind of ferritic stainless steel, composition by weight percent disclosed in Japan Patent JP10017999 are：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, composition by weight percent disclosed in Japan Patent JP 1986051012 are：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 the research of the anti-corrugation performance of deep-draw and surface during deep-draw.To improve ferritic stainless steel
Formability and anti-corrugation performance, generally use Nb, Ti bistable or the mono- Stabilizations of Ti, pass through improve strand equiax crystal
Rate improves single pass roughing and finish rolling reduction ratio, reduces finishing temperature and coiling temperature, increases hot rolled coil recrystallization annealing time
Number increases the measures such as cold rolling reduction ratio, cold rolled annealed, to obtain advantageous texture to improve formability.
Chinese patent CN98801478.5 disclose " deep drawing quality and the good ferritic stainless steel of resistance to ridging and
Its manufacturing method ", the patent in ferritic stainless steel mainly by adding Nb, Ti stabilizing element, to promote the analysis of TiN
Go out, and is matched by Ti and N certain product to control, and TiN promotes the formation of equiax crystal as the equiax crystal in liquid phase, into
And improve final texture, improve formability.
However, the steel grade involved by above-mentioned patent, relate generally to improve after punching press at the forming corrugation of ferritic stainless steel
Reason is not the processing for the ferritic stainless steel with good bending appearance.
Invention content
The purpose of the present invention is to provide a kind of ferritic stainless steels and its manufacturing method with good bending appearance, should
Ferritic stainless steel is expired by controlling ferrite grain size to the maximum extent with Nb stabilisations and optimum treatment process
The bending appearance of meaning, crystallite dimension≤20 μm in gained finished product ferritic stainless steel.Simultaneously as this stainless steel has well
Corrosion resistance, and be free of expensive alloying elements, it is at low cost.
In order to achieve the above objectives, the technical scheme is that：
By adding Nb stabilizing elements and using rational hot-roll annealing temperature and cold rolled annealed temperature, significantly refine
The crystallite dimension of ferritic stainless steel；Improve ferritic resistance to spot corrosion performance.Resistance to spot corrosion performance and atmospheric corrosion resistance reach
To 304 level.By Ca processing, brittle inclusion changes into the moulding field trash of low melting point.Flanging cracking is avoided.
Specifically, a kind of ferritic stainless steel with good bending appearance of the invention, chemical component weight percentage
Than for：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), remaining is Fe and inevitable impurity.
Further, crystallite dimension≤20 μm of the ferritic stainless steel.
In the composition design in the present invention with the ferritic stainless steel of good bending appearance：
The key for improving ferritic stainless steel bending surface orange peel phenomenon is crystal grain thinning.When crystal grain is sufficiently fine small, folding
Local deformation caused by curved will be evenly distributed among more crystal grain, and the deformation of each crystal grain is opposite to be reduced, intercrystalline
Relative slippage is reduced, and the surface of bending part is more smooth.In general, when ferritic stainless steel crystallite dimension is more than 50 μm
When, orange peel phenomenon will be generated during post-production, general acceptable crystallite dimension is 30 μm or so, but this is to electricity
For the application extremely harsh to appearance requirement such as ladder or household electrical appliances, still make us not satisfied enough.It is therefore desirable to further refine
Crystallite dimension.
But general ferritic stainless steel, in cold rolled annealed processing, Grain growth trend is larger, and ferrite crystal grain is tied again
It grows up quickly after crystalline substance.For Ti stabilizes ferritic stainless steel, TiN precipitate sizes are 3-5um, are grown up no tribute to crystal grain
It offers, and tiny precipitated phase TiC dissolves under higher annealing temperature, crystal grain can not be prevented to grow up.On the contrary, Nb can
For effectively fining ferrite grains, this pinning effect for being attributable to Nb (CN) and being dissolved Nb atom pair crystal boundaries.Except refinement
Except crystal grain effect, Nb also has various beneficial effects in ferritic stainless steel, can be former with the carbon in steel, nitrogen gap
Son, which combines, forms stable carboritride, it is suppressed that Cr23C6 crystal boundary precipitation, to improve corrosion resistance；Nb is at high temperature
It is solid-solution in ferrite matrix, by solution strengthening, ferritic stainless steel elevated temperature strength can be effectively improved.The present invention is fully sharp
With these beneficial effects of Nb elements, the ferritic stainless steel with good buckling performance has been invented.
In addition, the field trash conduplication side appearance of aluminium also has great influence.Larger field trash does not only result in steel surface and lacks
It falls into, and fine crack at flanging will be caused.Therefore, in VOD vacuum metlings, long-time argon gas stir process should be used, is made
In inclusion floating to slag, to reduce inclusion content；In continuous casting, the necessary condition of inclusion floating should be created, prevents two
Secondary oxidation；Using inclusions class, so that field trash is become the moulding of low melting point from brittle inclusion and be mingled with.
Cr：Cr is most important alloying element in stainless steel, and with the increase of Cr contents, stainless steel is in oxidizing acid media
Middle corrosion resistance, in Cl-Anticorrosion stress-resistant, spot corrosion, crevice corrosion ability are significantly increased in solution.To ensure to be developed ferrite
Stainless steel has a good corrosion resistance, and the Cr contents of ferritic stainless steel are limited in 18~22wt% in the present invention.
Cu：Cu can improve stainless steel corrosion resistance, significantly improve the cold forming capability of ferritic stainless steel, however excessive
Cu be easy annealing when with ε-Cu be precipitated, lead to the decline of cold-forming property and corrosion resistance.Therefore, Cu contents are limited in
0.3~0.5wt%.
Nb：Nb and C, N have very strong chemical combination, on the one hand, by forming stable Nb (CN) compound, prevent by
The corrosion proof decline caused by Cr concentration caused by the C compounds for forming Cr reduces, on the other hand, Nb is by being solid-solubilized in
In ferrite matrix, by hindering the fast growth of ferrite crystal grain in annealing process, strong fining ferrite grains, to subtract
Orange peel phenomenon in few bending process.Excessively high Nb will lead to the precipitation of Laves phases Fe2Nb, lead to penalty.Usually,
Minimized content in fixed steel needed for C, N atom should meet：Nb≥10(C+N).Thereby determine that Nb：0.3~0.6wt%.
C：C is harmful element in ferritic stainless steel.Since Cr contents are very high in alloy, and in ferrite C dissolving
Degree is more much lower than in austenite, thus is easy that M23C6 is precipitated on crystal boundary.It is such as precipitated higher than 800 DEG C or more, mostly with graininess
It is formed, brittleness is influenced little in crystal boundary；Such as at 600~700 DEG C, then alloy is set to become fragile with netted precipitation mostly on crystal boundary.
M23C6 on crystal boundary with netted speed of separating out quickly, not only alloy is made to become fragile, and cause serious crystal boundary because of the poor Cr of crystal boundary
Corrosion.Therefore, it is the intergranular corrosion resistance performance and toughness of improvement ferritic stainless steel, it is necessary to C content be reduced by smelting or adopted
It is fixed with strong C, N compound formation element.Since C can not possibly be removed completely, it is horizontal according to existing smelting equipment, it is specified that
C≤0.015wt%.
N：For N as harmful interstitial element, the solubility in ferrite is also very low, when alloy Cr contents are higher, holds
The easy corrosion resistance and toughness for generating Cr2N and reducing ferritic stainless steel, therefore, it is necessary to be removed as possible by smelting.Due to
N can not possibly be removed completely, according to existing smelting equipment level, it is specified that N≤0.020wt%.
Si：Si can be used as deoxidier, reducing agent in stainless steel, can effectively improve the high-temperature oxidation resistance of stainless steel
Can, it is plasticity Silicate Inclusions to be formed by field trash, smaller to the adverse effect of polishing performance.But excessive Si can lead to steel
Plasticity decline.Provide Si≤1.0wt%.
Mn：Mn is to expand austenitic area element, and excessive Mn can lead to duplex structure and make to add in ferritic stainless steel
Work degradation.Provide Mn≤1.0wt%.
P,S：P, S is impurity element in steel, reduces the high-temp plastic of steel, in ferritic stainless steel hot procedure,
The defects of easily and other factors one work and side are caused to be split.In addition, S can also reduce the pitting resistance of ferritic stainless steel.
Therefore, its content should be reduced as possible.
Al：Aluminium is kind of strong deoxidier when Al content reaches 0.005wt% in steel, you can plays deoxidation, but works as aluminium
When too high levels, being susceptible to alumina inclusion causes mold gap to block the surface squama folding defect with final products, therefore
Provide Al content between 0.005~0.06wt%.
Ca：When Ca contents are more than 0.0010wt% in steel, magnesium aluminate spinel class brittle inclusion can effectively be made to be denaturalized,
Formed it is moulding be mingled with, improve surface polishing performance.But Ca contents, when being more than 0.0050wt%, being formed by calcic field trash will
Reduce the corrosion resistance of ferritic stainless steel.Therefore, the content of calcium is 0.0010~0.0050wt%.
A kind of manufacturing method of ferritic stainless steel with good bending appearance of the present invention, includes the following steps：
1) it smelts, cast
Ferritic stainless steel, chemical component weight percentage are：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), remaining is for Fe and inevitably
Impurity；By mentioned component smelt and by pouring molten steel at strand；
2) hot rolling, batch
By heating strand to roughing is carried out after 1100~1180 DEG C, finish rolling is completed at 750~850 DEG C, at 600~650 DEG C
It is batched, obtains coil of strip；
3) uncoiling, annealing, pickling
Steel band, 950~1000 DEG C of annealing temperature, per mm of thickness strip anneal soaking time 1 are obtained after gained coil of strip uncoiling
~3min；
4) cold rolling
Cold roling reduction 75%~80%；
5) recrystallization annealing
950~1000 DEG C of annealing temperature, per mm of thickness strip anneal 1~3min of soaking time, ferrite grain size
≤ 20 μm, obtaining finished product has the ferritic stainless steel of good bending appearance.
Further, in step 3), steel band 25~40m/min of the speed of service in annealing furnace.
In addition, gained finished product has crystallite dimension≤20 μm of the ferritic stainless steel of good bending appearance.Gained finished product has
It is 320~370mv to have the pitting potential of the ferritic stainless steel of good bending appearance.
The beneficial effects of the present invention are：
A) it by adding Nb stabilizing elements and using rational hot-roll annealing temperature and cold rolled annealed temperature, significantly refines
The crystallite dimension of ferritic stainless steel, average grain size≤20 μm；
B) refinement of ferrite stainless crystalline grain of steel significantly improves bending appearance；
C) by adding Nb stabilizing elements, ferritic resistance to spot corrosion performance is improved.Resistance to spot corrosion performance and resistance to big
Gas corrosion has reached 304 level；
D) by Ca processing, brittle inclusion changes into the moulding field trash of low melting point.Flanging cracking is avoided.
Description of the drawings
Fig. 1 be 1 steel grade of the embodiment of the present invention crystal grain orientation maps andODF sectional views.
Fig. 2 be 2 steel grade of comparative example crystal grain orientation maps andODF sectional views.
Fig. 3 is 1 steel grade of the embodiment of the present invention with the steel grade grain structure figure that 200 μm are that scale obtains.
Fig. 4 is 2 steel grade of comparative example with the steel grade grain structure figure that 100 μm are that scale obtains.
Fig. 5 is 1 steel grade bending appearance figure of the embodiment of the present invention.
Fig. 6 is 2 steel grade bending appearance figure of comparative example.
Fig. 7 is 1 steel grade ferrite grain size distribution map of the embodiment of the present invention.
Fig. 8 is 2 steel grade ferrite grain size distribution map of comparative example.
Fig. 9 is 1 steel grade of the embodiment of the present invention, 18 period accelerated corrosion photos.
Figure 10 is 2 steel grade of comparative example, 18 period accelerated corrosion photos.
Figure 11 is 304 steel, 18 period accelerated corrosion photos.
Specific implementation mode
With reference to embodiment and attached drawing, the present invention will be further described.
The embodiment of the present invention has ferritic stainless steel and comparative example steel grade chemical composition such as 1 institute of table of good bending appearance
Show, remaining is Fe and inevitable impurity.The embodiment of the present invention compares as shown in table 2 with comparative example key process parameter.
1. embodiment of the present invention of table 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 |
2. embodiment of the present invention of table is compareed with comparative example key process parameter
To improve the bending effect that embodiment 1 is intended to finished product ferritic stainless steel, three kinds of different cold rolling reductions are selected
60%, 70% and 80% and three it is cold move back 920 DEG C, 950 DEG C and 980 DEG C of temperature, research cold rolling reduction moves back recrystallization to cold
The influence of situation and bending effect.
Using it is identical it is cold move back 920 DEG C of temperature when, a small amount of recrystallization has occurred in deflection 60%, 70% sample, the overwhelming majority
For ribbon tissue, and 80% deflection sample perfect recrystallization；After annealing temperature is increased to 950 DEG C and 980 DEG C, three kinds of cold rollings
After deflection 60%, 70% and 80% can recrystallize, but 60% cold rolling reduction sample crystallite dimension is significantly greater than
The two.
Bending is the experimental results showed that when cold rolling reduction is 80%, and crystallite dimension is minimum, and orange peel is most slight after bending.Crystal grain
The reason of size has great influence to bending effect is as follows：When carrying out flanging deformation, each intercrystalline compatible deformation, deflection
It is assigned to each crystal grain of bending part, under the tiny situation of crystal grain, the deformation quantity that unit die is born becomes smaller, single
A crystal grain Dislocations sliding deformation amount is reduced, and roughness reduces, and the place naked eyes of such flanging look and seem finer and closely woven, and orange peel is more
Slightly.
On the contrary, can seem rougher if coarse grains, at flanging.Above-mentioned test result illustrates that use is larger
Cold rolling reduction, obtain tiny ferrite crystal grain, contribute to improve product bending it is anti-corrugation and resist coarse performance, cold rolling become
When shape amount is 80%, bending appearance is best.
Table 3 is that the mechanical property of the embodiment of the present invention and comparative example, the r values for characterizing forming property and corresponding ferrite are brilliant
Particle size.It can be seen that the r values of the mechanical property of the two, characterization forming property have no too big difference, but crystallite dimension is significantly different,
Embodiment crystal grain is more tiny.This is attributable to the effect of embodiment higher Nb contents, that is, is dissolved the niobium of state and the second phase of niobium
Particle is easy the segregation on crystal boundary, sub boundary and dislocation line, effectively prevents the movement of crystal boundary, sub boundary and dislocation, delays
It carries out to recrystallization process, to prevent growing up for crystal grain.Within the scope of the present invention, Nb contents are higher, this refining effect
It is more notable.
The mechanical property and average grain size of 3 embodiment of the present invention of table and comparative example compare
Fig. 1 be 1 steel grade of the embodiment of the present invention crystal grain orientation maps andODF sectional views.As seen from Figure 1,
The texture of embodiment 1 is substantially { 111 } γ texture, and crystal grain is orientated the similar continuous river of wire shaped, shows brilliant in steel grade
Grain is orientated and is uniformly distributed along γ lines, does not occur concentrating situation.The γ texture of different orientation advantageously reduces the anisotropic of steel,
Intensity is not much different, and is more advantageous to compatible deformation, i.e. appearance after steel grade bending is more preferable.
Fig. 2 be 2 steel grade of comparative example of the present invention crystal grain orientation maps andODF sectional views.From Figure 2 it can be seen that
2 steel grade of comparative example has stronger { 111 }<112>γ texture, crystal grain are orientated the similar hills independent one by one of wire shaped, table
Crystal grain was orientated to concentrate in bright steel grade, caused anisotropic stronger, there is also the α texture of a small amount of ratio, and α texture is to steel grade
Bending and forming and corrugation performance are unfavorable.Therefore, the embodiment of the present invention has more preferably forming property and anti-corrugation performance.
Fig. 3 is 1 steel grade of the embodiment of the present invention with the steel grade grain structure figure that 200 μm are that scale obtains.Fig. 4 is comparative example 2
The steel grade grain structure figure that steel grade is obtained with 100 μm for scale.Through Fig. 3, Fig. 4 comparison it is found that under same scale size, this hair
1 steel grade crystallite dimension of bright embodiment is obviously more refined than 2 steel grade crystallite dimension of comparative example.
1 steel grade bending appearance of the embodiment of the present invention is as shown in Figure 5.2 steel grade bending appearance such as Fig. 6 institutes of comparative example
Show.Two steel grades carry out Bending Processing with elevator plate processing technology, it can be seen that the bending part of 2 steel grade of comparative example is whitened area
Domain is wider and bending part is more coarse；And the bending part of 1 steel grade of the embodiment of the present invention is smooth, fine and smooth, appearance is much better than pair
Ratio 2.
Ferrite grain size directly influences bending appearance.When crystallite dimension is 35-60um, orange peel is serious, can not
Receive；When crystallite dimension is 20~35um, orange peel is lighter, is subjected to；Crystallite dimension is less than 20um, and orange peel is very light, outside bending
It sees good.
Fig. 7 is 1 steel grade ferrite grain size distribution map of the embodiment of the present invention.Fig. 8 is 2 steel grade ferrite crystal grain of comparative example
Size distribution plot.By contrast it is found that 1 steel grade ferrite grain size of the embodiment of the present invention has focused largely on less than or equal to 20 μm
Region, average grain size are 16 μm.And 2 steel grade ferrite grain size of comparative example focuses mostly on greatly the region of 20 μm of >, it is average
Crystallite dimension is 29 μm, this flanging appearance for directly resulting in 1 steel grade of the embodiment of the present invention is substantially better than 2 steel grade of comparative example.
Table 4 is the pitting potential comparison of the embodiment of the present invention and comparative example.As shown in Table 4, the embodiment of the present invention and comparison
The pitting potential of example steel grade has all reached the levels of 304 stainless steels, but the point of the higher steel grade of the embodiment of the present invention of amount containing Nb
Erosion current potential is apparently higher than the low comparative example steel grade of amount containing Nb.This is equally attributable to the effect of Nb.On the one hand, Nb is combined with C, N,
Form Nb (CN), it is suppressed that the precipitation of M23C6 phases avoids the poor Cr of crystal boundary.On the other hand, as amount containing Nb improves, ferrite
Solid solution Nb contents in matrix increase, and lead to the further segregation of grain boundaries Nb atoms, and then result in enrichments of the Cr in crystal boundary.This
Two aspect factors, which result in steel grade of the embodiment of the present invention, has higher pitting potential.
The pitting potential of 4. embodiment of the present invention of table and comparative example compares
| 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 experiment can preferably compare corrosion proof difference.
Specimen surface is polished with #600 sand paper, and the test period is 30, and each period is carried out in three steps, 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 1 steel grade of the embodiment of the present invention, 18 period accelerated corrosion photos.Figure 10 is comparative example 18 periods of 2 steel grade
Accelerated corrosion photo.Figure 11 is 304 steel grade, 18 period accelerated corrosion photos.In Fig. 9,1 18 week of steel grade of the embodiment of the present invention
After phase accelerates corruption, the smooth and bright like a mirror face in surface can form such as mirror reflection effect on surface.And 2 steel grade of comparative example and 304 steel grades
After 18 periods accelerate corruption, surface is obviously dirty, has no reflecting effect.It can be seen that the corrosion resistance of 1 steel grade of the embodiment of the present invention is better than
Comparative example 2 and 304 steel grades.
As described above, using the present invention can provide a kind of good high Cr ferritic stainless steels of bending appearance, this iron elements
Body stainless steel have with the comparable corrosion resistance of 304 stainless steels, have broad application prospects in elevator and household electric appliances.
It should be noted that the above examples are only used to illustrate the technical scheme of the present invention and are not limiting.Although with reference to compared with
Good embodiment describes the invention in detail, it will be understood by those of ordinary skill in the art that, it can be to the technology of invention
Scheme is modified or replaced equivalently, and without departing from the range of technical solution of the present invention, should all cover the power in the present invention
In sharp claimed range.
Claims (4)
1. a kind of ferritic stainless steel with good bending appearance, chemical component weight percentage are：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), remaining is Fe and inevitable impurity；Crystallite dimension≤20 μm of the ferritic stainless steel.
2. a kind of manufacturing method of the ferritic stainless steel with good bending appearance, includes the following steps：
1) it smelts, cast
Ferritic stainless steel, chemical component weight percentage are：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), remaining is Fe and can not
The impurity avoided；It is smelted by mentioned component and is cast into strand；
2) hot rolling, batch
By heating strand to roughing is carried out after 1100~1180 DEG C, finish rolling is completed at 750~850 DEG C, is carried out at 600~650 DEG C
It batches, obtains coil of strip；
3) uncoiling, annealing, pickling
After gained coil of strip uncoiling steel band, 950~1000 DEG C of annealing temperature, per mm of thickness strip anneal soaking time 1~
3min；
4) cold rolling
Cold roling reduction 75%~80%；
5) recrystallization annealing
950~1000 DEG C of annealing temperature, per mm of thickness strip anneal 1~3min of soaking time, the μ of ferrite grain size≤20
M, obtaining finished product has the ferritic stainless steel of good bending appearance.
3. manufacturing method according to claim 2, which is characterized in that in step 3), the steel band is run in annealing furnace
25~40m/min of speed.
4. manufacturing method according to claim 2, which is characterized in that gained finished product has the ferrite of good bending appearance
The pitting potential of stainless steel 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 |
| CN112501513B (en) * | 2020-11-30 | 2022-05-13 | 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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| CN101899625B (en) * | 2009-05-25 | 2012-05-30 | 宝山钢铁股份有限公司 | Ferrite stainless steel and manufacturing method thereof |
| CN103510013B (en) * | 2013-09-29 | 2018-06-05 | 宝钢不锈钢有限公司 | The stanniferous ferritic stainless steel and its manufacturing method of a kind of good wrinkle resistance |
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Effective date of registration: 20190823 Address after: The Hong Kong Industrial Zone in Luoyuan Bay Development Zone of Luoyuan County of Fuzhou City, Fujian province 350600 Patentee after: Baosteel Desheng Stainless Steel Co., Ltd. Address before: 735 Baoshan District Changjiang Road, Shanghai, No. 200431 Patentee before: Baosteel Stainless Steel Co.,Ltd. |