CN105331899A - Ferritic stainless steel with good crease resistance and manufacturing method of ferritic stainless steel - Google Patents
Ferritic stainless steel with good crease resistance and manufacturing method of ferritic stainless steel Download PDFInfo
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- CN105331899A CN105331899A CN201510615653.5A CN201510615653A CN105331899A CN 105331899 A CN105331899 A CN 105331899A CN 201510615653 A CN201510615653 A CN 201510615653A CN 105331899 A CN105331899 A CN 105331899A
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- stainless steel
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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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
The invention provides ferritic stainless steel with good crease resistance and a manufacturing method of the ferritic stainless steel. The steel comprises, by mass, 0.02%-0.08% of C, 0.02%-0.08 % of N, 0.05%-0.60% of Si, 0.05%-0.50% of Mn, 12.0%-19.0% of Cr, 0.1%-1.0% of Cu, 0.1%-2.0% of Ni, less than 0.05% of P, less than 0.02% of S and the balance Fe and inevitable impurities. The elements mentioned above satisfy the relation (please see the inequation in the specific specification). High-temperature short-time annealing is conducted after the steel is hot-rolled, the steel is then subjected to cold rolling and recrystallization annealing, grains of different texture orientations in a finished product sheet are randomly distributed, the wrinkling height is below 15 micrometers, and the good crease resistance is obtained.
Description
Technical field
The present invention relates to ferritic stainless steel, be specifically related to a kind of ferritic stainless steel and the manufacture method thereof with good anti-wrinkling performance.
Background technology
Ferritic stainless steel does not contain or only containing a small amount of nickel, cost is lower, and it has good stamping formabilily concurrently simultaneously, is therefore widely used in buildings, household electrical appliance, kitchen tackle, all respects in the life such as auto exhaust.But because ferrite stainless steel matrix is BCC body-centered cubic structure, obvious punching press ridging defect is there is in punching course, need to increase extra polishing cost, also serious polishing dust can be caused to pollute simultaneously, limit the widespread use of ferritic stainless steel, therefore, the wrinkling height of punching press reducing ferrite stainless steel sheet becomes the technical barrier being badly in need of at present solving.
The wrinkling a kind of surface imperfection being ferritic stainless steel and producing when dependent variable is larger in forming process, this defect occurs in the rolling direction being parallel to plate, shows as narrow convex stripe, i.e. surperficial fold.The wrinkling outward appearance destroying molded component, eliminating it needs expensive grinding and polishing operation.Wrinkling be due to extend in parallel from the rolling direction of steel plate, the viscous deformation of crystal grain group that crystal orientation is near is different and produce, and is alternatively flowed by the Anisotropic Plastic of mixing texture to cause.Therefore, low wrinkling height be obtained, need the crystal grain stochastic distribution in thin plate with different orientation.
Chinese patent 98801478.5 adds mainly through stabilizing element niobium titanium compound, and set Ti/N content ratio and be greater than 12, Nb and V total content is less than 0.1% and meets V/Nb=2-5 simultaneously, simultaneously by hot rolling heating and temperature control below 1170 DEG C, more than 950 DEG C, complete rough rolling process, and then obtain low wrinkling height.Chinese patent 200910048291.0 adopts single Nb to stablize ferritic stainless steel, forms niobium carbonitrides precipitated phase, and imparts corresponding metallurgical technology system: high roughing temperature and low finishing temperature, thus reduces the surface wrinkling of cold-reduced sheet.In Chinese patent CN00800983.X, when not pursuing ultra-low carbon nitrogen atom, with the addition of V element to meet: 0.06≤(C+N)≤0.12,1≤C/N, and then meet 1.5 × 10-3≤(V × N)≤1.5 × 10-2, obtain lower corrugation height by the control of composition.Chinese patent 200680049702.2 by accurately controlling the concentration of the aluminate in molten steel, and adds stabilizing element Ti, is improved the ratio of the equiax crystal in slab, and then obtain low wrinkling height by the effect of TiN.Therefore, prior art emphasis reduces corrugation height in the interpolation of the stabilizing elements such as Nb, Ti, V, Al, and technology controlling and process plays booster action, and the high-temperature phase-change all not relating to ferritic stainless steel is theoretical.
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 anti-wrinkling performance, make the crystal grain stochastic distribution in final finished thin plate with different texture orientation, thus obtain extremely low wrinkling height, and improve the tensile strength of steel.
For achieving the above object, technical scheme of the present invention is:
A kind of ferritic stainless steel with good anti-wrinkling performance, its chemical composition mass percent is: C:0.02 ~ 0.08%, N:0.02 ~ 0.08%, Si:0.05 ~ 0.60%, Mn:0.05 ~ 0.50%, Cr:12.0 ~ 19.0%, Cu:0.1 ~ 1.0%, Ni:0.1 ~ 2.0%, P<0.05%, S<0.02%, all the other are Fe and inevitable impurity; And above-mentioned element needs satisfied following relation simultaneously:
Further, the wrinkling height of described ferritic stainless steel is below 15 μm.
In Composition Design of the present invention:
C: a lot of shortcomings on ferrite stainless Steel Properties, such as: ductile-brittle transition temperature is high, notch sensitivity is large, and solidity to corrosion difference is all relevant with the carbon in steel.But carbon is austenite former, plays a crucial role in the present invention, its content can not be too low, so lower limit is set to 0.02%, but too high levels, can worsen the performance of ferritic stainless steel, therefore, it is 0.02 ~ 0.08% that the present invention controls C content.
N: the same with C, N are also austenite former, play a crucial role in the present invention, and too high levels can cause the decline of stainless steel plasticity and erosion resistance, therefore, and the present invention's control N0.08 ~ 0.02%.Being added with in right amount of C, N content is beneficial to increases austenitic ratio under hot conditions of the present invention, and then is conducive to the improvement of wrinkling performance.
Si: solution strengthening element, the increase of its content can cause the decline of unit elongation and toughness, and its content is more few better, and its upper limit is set as 0.6%, but Si adds as deoxidant element sometimes, considers smelting cost simultaneously, and its lower limit set is 0.05%.Therefore, the present invention's control Si content is 0.05 ~ 0.6%.
Mn: weak austenite former, is also solution strengthening element simultaneously, can suppress the deleterious effect of sulphur in steel, but its content increase can worsens corrosive nature, and therefore Mn content needs to control below 0.5%.
Cu: similar with Mn, Cu are austenite former, can improve the erosion resistance of steel grade, expand stainless steel high temperature austenite content, be added with in right amount to be beneficial to and improve punching performance, but excessive interpolation can worsen processing characteristics, therefore the present invention's control Cu content is 0.1 ~ 1.0%.
Cr: the principal element improving erosion resistance, the increase of its content obviously can strengthen the erosion resistance at oxidizing acid, improve its anticorrosion stress-resistant in chloride soln, spot corrosion and crevice corrosion behavior, but the increase of its content can cause again the reduction of toughness and processibility, therefore, the present invention's control Cr content is 12 ~ 19%.
P and S: be harmful element, P is harmful for hot workability, and S can be separated at crystal edge, and crystal edge is become fragile, and the formation of MnS is also to the solidity to corrosion of steel and harmful in addition.Therefore the content of P and S should be as far as possible on the low side on the basis of existing steel making ability.Therefore, control P<0.05%, S<0.02%.
Ni: in the ferritic stainless steel of routine, Ni content is few, but Ni is as austenite former, corrosion resistance nature can be improved on the one hand, effectively can expand the austenite ratio under ferritic stainless steel high temperature on the other hand, make full use of thermal treatment process and promote that austenite is to martensitic transformation, and then obtain low texture intensity, and make the crystal grain randomization of various different orientation, the wrinkling height after final reduction Sheet stretch.But when Ni too high levels, risk is split on the limit that can increase in ferritic stainless steel hot-rolling process, and therefore, the present invention's control Ni content is 0.1 ~ 2.0%.
Meanwhile, in order to austenitic ratio under ensureing high temperature, need to meet simultaneously
(wherein, the symbol of element represents mass percent × 100 of respective element), in the present invention, C, N and Ni are austenite former, control
contribute to expanding high temperature austenite ratio, thus ensure that follow-up hot-roll annealing completes between two-phase region, make full use of high temperature austenite to phase transformation Texture evolution during ferritic transformation, and then inhibit the formation of hot rolling deformation texture, finally be conducive to the crystal grain stochastic distribution of various different orientation, obtain low wrinkling height.And the peak mole ratio of ferritic stainless steel high temperature austenite of the present invention is greater than 30%.
The manufacture method with the ferritic stainless steel of good anti-wrinkling performance of the present invention, it comprises the steps:
1) smelt, forge
Undertaken smelting, being forged into slab by following chemical composition; Described chemical composition mass percent is: C:0.02 ~ 0.08%, N:0.02 ~ 0.08%, Si:0.05 ~ 0.60%, Mn:0.05 ~ 0.50%, Cr:12.0 ~ 19.0%, Cu:0.1 ~ 1.0%, Ni:0.1 ~ 2.0%, P<0.05%, S<0.02%, all the other are Fe and inevitable impurity; And above-mentioned element needs satisfied following relation simultaneously:
2) hot rolling
Heating temperature≤1200 DEG C, finishing temperature is 800 ~ 900 DEG C;
3) hot-roll annealing
Hot-roll annealing temperature is 900 ~ 1050 DEG C, annealing time 5 ~ 6min;
4) cold rolling
Cold rolling draft > 70%;
5) cold rolling after annealing
Cold rolling after annealing temperature is 850 ~ 1000 DEG C, annealing time 1 ~ 2min, and controls average grain size below 20 μm.
In design and manufacture technology of the present invention:
Hot rolling heating and temperature control of the present invention is below 1200 DEG C, finishing temperature is between 800 ~ 900 DEG C, the reduction of finishing temperature is conducive to the recrystallize, the grain refining that promote hot-rolled sheet, be conducive to wrinkling improved performance, the increase of resistance to deformation when but too low finishing temperature can cause rolling, simultaneously due to the increase of the difference of top layer shearing strain and central core plane deformation during rolling, gradient is excessive in a thickness direction to cause hot-rolled sheet microtexture, cause serious wrinkling, therefore finishing temperature control is more than 800 DEG C.
Hot-roll annealing is critical process of the present invention, and what traditional technology adopted is that ferrite carries out anneal below austenite transition points, avoids entering between austenite and ferritic two-phase region.Containing higher carbon nitrogen austenitic forming element in steel of the present invention, and add a small amount of Ni, therefore be all two-phase structure under high temperature, in order to obtain low wrinkling height, make full use of phase transformation and make texture randomization theoretical, hot-roll annealing must complete in two-phase region, in order to make the effect of phase transformation larger, need to carry out annealing between high temperature, short time in the temperature that austenite content is maximum, therefore set annealing temperature more than 900 DEG C, this is the maximum difference of the present invention with traditional technology.In addition, if annealing temperature is more than 1050 DEG C, ferrite crystal grain abnormal growth, is also difficult to realize the refinement of finished product lath grain even if increase cold rolling draft, causes the increase of surfaceness, and simultaneous temperature is too high increases on-the-spot suitability for industrialized production difficulty.Therefore, the present invention controls hot-roll annealing interval is 900 ~ 1050 DEG C.
The present invention sets cold rolling draft and is greater than 70%, wants to obtain low wrinkling height, and realizes production board homogeneity of structure, must have corresponding cold rolling draft, but too high draft can increase again the load of milling train, causes production difficulty very big.
Cold rolling after annealing is in the final stage of metallurgical technology flow process, needs suitable temperature to carry out final annealing.If cold rolling after annealing temperature is too low, be difficult to obtain recrystallize completely, easily occur obvious mixed crystal; For ferritic stainless steel, cold rolling after annealing temperature is too high also can cause the too thick of crystal grain, causes grain-boundary weakness and surfaceness to increase.Therefore, cold rolling after annealing thermal creep stress between 850 ~ 1000 DEG C, and controls average grain size below 20 μm.
The present invention is mainly through optimizing ferritic stainless steel alloy composition, make full use of the limited phase transformation of ferritic stainless steel high temperature, appropriate design hot-roll annealing technique, and in conjunction with follow-up cold rolling rules and recrystallization annealing system, make the crystal grain stochastic distribution in final finished thin plate with different texture orientation, thus obtain extremely low wrinkling height after the stretch.
Beneficial effect of the present invention:
The present invention is by the appropriate interpolation of C, N and Ni austenite former, and the limited phase transformation of high temperature made full use of in steel of the present invention, not only increase the anti-wrinkling performance of ferritic stainless steel, higher tensile strength can also be obtained, expand the range of application of ferritic stainless steel further.
Have the crystal grain stochastic distribution of different texture orientation in final finished thin plate of the present invention, wrinkling height is below 15 μm, and wrinkling grade is excellent, obtains excellent anti-wrinkling performance.
Accompanying drawing explanation
Fig. 1 is the balance stable state phasor of the embodiment of the present invention 2 that Thermo-Calc calculates, and wherein, numbering 1 is ferritic phase content; Numbering 4 is the change of austenite phase content.
Embodiment
Below in conjunction with embodiment and accompanying drawing, the present invention will be further described.
Table 1 is the composition of embodiment of the present invention steel and comparative example steel, and table 2 is the manufacturing process of the embodiment of the present invention and comparative example steel, and table 2 is the performance of the embodiment of the present invention and comparative example steel.
Undertaken smelting by composition shown in table 1 and be forged into slab (35mm is thick), then control according to above-mentioned metallurgical manufacturing process, heat slab, the hot-rolled steel sheet that thickness of slab is 3 ~ 5mm is made in the hot rolling through 3-6 passage; Then through hot rolling intermediate annealing process, then annealed sheet is carried out pickling to remove the iron scale on surface, after under multi-pass cold rolling, carry out final cold rolling after annealing, manufacture the goods that thickness of slab is 0.6 ~ 2mm, concrete technology parameter is as shown in table 2.By metallographic structure determination recrystal grain size, cold rolled annealed rear average grain size is below 20 μm.
Sample is intercepted along in rolling direction at production board, and the tension specimen preliminary draft 25% of being processed into Japanese JIS5 standard then with surface roughometer perpendicular to rolling direction being measured its wrinkling height Pt (difference of altitude of crest and trough), measuring distance is 4mm.Pt value is excellent below 15 μm, be good at 15 ~ 20 μm, and 20 ~ 30 μm are, more than 30 μm for poor.Finally, situation assembled by the crystal grain bunch being analyzed production board vertical section by EBSD: in steel, the composition of microcosmic texture and distribution situation adopt EBSD (EBSD) to resolve, { 001} orientation flocks together, and the length along rolling direction is greater than 5 grain-sizes, be just judged to be that { 001} crystal grain bunch is assembled.Concrete outcome is as shown in table 2.
As shown in Table 2, have the crystal grain stochastic distribution of different orientation in the ferritic stainless steel that manufacture of the present invention obtains, wrinkling height is below 15 μm, and wrinkling grade is excellent, obtains excellent anti-wrinkling performance.
As shown in Figure 1, be between high temperature austenite+ferrite two-phase region at 860 ~ 1240 DEG C, 950 DEG C time, austenite ratio is maximum, therefore, annealing after hot rolling of the present invention completes between two-phase region, ensure that the effect of phase transformation is larger, makes final cold rolled sheet can obtain best anti-wrinkling performance.
Table 1 unit: wt%
| C | Si | Mn | P | S | Cr | Ni | Cu | N | |
| Embodiment 1 | 0.030 | 0.10 | 0.21 | 0.02 | 0.004 | 12.83 | 0.11 | 0.13 | 0.025 |
| Embodiment 2 | 0.045 | 0.29 | 0.49 | 0.02 | 0.003 | 16.13 | 0.32 | 0.09 | 0.039 |
| Embodiment 3 | 0.073 | 0.49 | 0.31 | 0.01 | 0.003 | 17.24 | 0.84 | 0.86 | 0.035 |
| Embodiment 4 | 0.038 | 0.56 | 0.15 | 0.03 | 0.001 | 18.79 | 1.28 | 0.42 | 0.072 |
| Comparative example 1 | 0.012 | 0.51 | 0.24 | 0.01 | 0.006 | 12.59 | 0.10 | 0.25 | 0.015 |
| Comparative example 2 | 0.015 | 0.27 | 0.33 | 0.02 | 0.004 | 18.39 | 0.15 | 0.18 | 0.014 |
Table 2
Remarks: ×: { 001} crystal grain bunch is assembled; Zero: { 001} crystal grain Dispersed precipitate.
Claims (4)
1. one kind has the ferritic stainless steel of good anti-wrinkling performance, its chemical composition mass percent is: C:0.02 ~ 0.08%, N:0.02 ~ 0.08%, Si:0.05 ~ 0.60%, Mn:0.05 ~ 0.50%, Cr:12.0 ~ 19.0%, Cu:0.1 ~ 1.0%, Ni:0.1 ~ 2.0%, P<0.05%, S<0.02%, all the other are Fe and inevitable impurity; And above-mentioned element needs satisfied following relation simultaneously:
2. the ferritic stainless steel with good anti-wrinkling performance according to claim 1, it is characterized in that, the wrinkling height of described ferritic stainless steel is below 15 μm.
3. have a manufacture method for the ferritic stainless steel of good anti-wrinkling performance, it comprises the steps:
1) smelt, forge
Undertaken smelting, being forged into slab by following chemical composition; Described chemical composition mass percent is: C:0.02 ~ 0.08%, N:0.02 ~ 0.08%, Si:0.05 ~ 0.60%, Mn:0.05 ~ 0.50%, Cr:12.0 ~ 19.0%, Cu:0.1 ~ 1.0%, Ni:0.1 ~ 2.0%, P<0.05%, S<0.02%, all the other are Fe and inevitable impurity; And above-mentioned element needs satisfied following relation simultaneously:
2) hot rolling
Heating temperature≤1200 DEG C, finishing temperature is 800 ~ 900 DEG C;
3) hot-roll annealing
Hot-roll annealing temperature is 900 ~ 1050 DEG C, annealing time 5 ~ 6min;
4) cold rolling
Cold rolling draft > 70%;
5) cold rolling after annealing
Cold rolling after annealing temperature is 850 ~ 1000 DEG C, annealing time 1 ~ 2min, and controls average grain size below 20 μm.
4. the manufacture method with the ferritic stainless steel of good anti-wrinkling performance according to claim 3, it is characterized in that, the wrinkling height of described ferritic stainless steel is below 15 μm.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109536690A (en) * | 2018-10-12 | 2019-03-29 | 甘肃酒钢集团宏兴钢铁股份有限公司 | A kind of coexistence region heat treatment process of ferritic stainless steel hot-rolling strip |
| EP3594372A4 (en) * | 2017-04-25 | 2020-01-22 | JFE Steel Corporation | Material for cold-rolled stainless steel sheet, and production method therefor |
| CN110724809A (en) * | 2019-11-18 | 2020-01-24 | 东北大学 | Method for controlling grain size uniformity of hot-rolled high-carbon austenitic stainless steel |
| CN111936654A (en) * | 2018-03-30 | 2020-11-13 | 日铁不锈钢株式会社 | Ferritic stainless steel having excellent ridging resistance |
| CN111944973A (en) * | 2019-05-17 | 2020-11-17 | 南京理工大学 | Preparation method of heterogeneous layered structure duplex stainless steel |
| CN112725700A (en) * | 2020-12-28 | 2021-04-30 | 鸿富晋精密工业（太原）有限公司 | Metal part and machining method thereof |
| CN113604639A (en) * | 2021-08-09 | 2021-11-05 | 长春工业大学 | Heat treatment method for improving surface wrinkling of phase-change ferrite stainless steel |
| CN115591993A (en) * | 2022-10-31 | 2023-01-13 | 广州大学（Cn） | Method for eliminating ferrite stainless steel wrinkles on outer wall formed by composite board punch forming |
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| JP2010270399A (en) * | 2010-07-08 | 2010-12-02 | Nippon Metal Ind Co Ltd | Method for manufacturing ferritic-stainless steel excellent in ridging resistance |
| 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 |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2010270399A (en) * | 2010-07-08 | 2010-12-02 | Nippon Metal Ind Co Ltd | Method for manufacturing ferritic-stainless steel excellent in ridging resistance |
| 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 |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP3594372A4 (en) * | 2017-04-25 | 2020-01-22 | JFE Steel Corporation | Material for cold-rolled stainless steel sheet, and production method therefor |
| CN111936654A (en) * | 2018-03-30 | 2020-11-13 | 日铁不锈钢株式会社 | Ferritic stainless steel having excellent ridging resistance |
| CN109536690A (en) * | 2018-10-12 | 2019-03-29 | 甘肃酒钢集团宏兴钢铁股份有限公司 | A kind of coexistence region heat treatment process of ferritic stainless steel hot-rolling strip |
| CN111944973A (en) * | 2019-05-17 | 2020-11-17 | 南京理工大学 | Preparation method of heterogeneous layered structure duplex stainless steel |
| CN110724809A (en) * | 2019-11-18 | 2020-01-24 | 东北大学 | Method for controlling grain size uniformity of hot-rolled high-carbon austenitic stainless steel |
| CN110724809B (en) * | 2019-11-18 | 2021-05-25 | 东北大学 | Method for controlling grain size uniformity of hot-rolled high-carbon austenitic stainless steel |
| CN112725700A (en) * | 2020-12-28 | 2021-04-30 | 鸿富晋精密工业（太原）有限公司 | Metal part and machining method thereof |
| CN113604639A (en) * | 2021-08-09 | 2021-11-05 | 长春工业大学 | Heat treatment method for improving surface wrinkling of phase-change ferrite stainless steel |
| CN115591993A (en) * | 2022-10-31 | 2023-01-13 | 广州大学（Cn） | Method for eliminating ferrite stainless steel wrinkles on outer wall formed by composite board punch forming |
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