CN113604639A - Heat treatment method for improving surface wrinkling of phase-change ferrite stainless steel - Google Patents
Heat treatment method for improving surface wrinkling of phase-change ferrite stainless steel Download PDFInfo
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- 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
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- 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
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C21D2211/005—Ferrite
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
A heat treatment method for improving surface wrinkling of phase-change ferritic stainless steel comprises the following steps: (1) smelting molten steel to prepare a continuous casting billet, wherein the components of the continuous casting billet comprise, by mass, 0.03-0.13% of C, 0.2-1.2% of Si, 0.2-0.6% of Mn, less than or equal to 0.008% of S, less than or equal to 0.04% of P, less than or equal to 0.04% of N, 12.00-20.00% of Cr and the balance of Fe; (2) hot rolling at 1150-1250 ℃ with a total reduction rate of 60-95% at the start rolling temperature, and air cooling; (3) annealing at 800-1150 ℃, and water quenching to room temperature; (4) cold rolling; (5) and carrying out secondary annealing at 870-1080 ℃ and air cooling. The annealing treatment is carried out before the cold rolling of the phase-changeable ferritic stainless steel, martensite is introduced into the stainless steel through the quenching treatment, the formation of an aggregated structure in the cold-rolled annealed strip steel is inhibited, the wrinkle phenomenon of the stainless steel in the processes of stamping and drawing is reduced, and the structure performance and the quality effect of products of the ferritic stainless steel are improved.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to a heat treatment method for improving surface wrinkling of phase-change ferrite stainless steel.
Background
Austenitic stainless steel is widely used in the industrial field due to its excellent corrosion resistance and good formability, but austenitic stainless steel has high Ni content and relatively high cost, so Ni-saving ferritic stainless steel is more and more paid attention by researchers.
The ferritic stainless steel is low in cost, has high heat conductivity coefficient, high-temperature corrosion resistance, high-temperature oxidation resistance and other excellent performances, and is widely applied to the fields of kitchenware, household appliances, decoration and the like. Although ferritic stainless steel has many advantages compared with austenitic stainless steel, the forming performance of ferritic stainless steel is far from the level of austenitic stainless steel, which is mainly reflected in that wrinkles appear on the surface of stainless steel during cold working, and the use and processing cost is seriously influenced. At present, the wrinkling defect is generally considered to be generated due to the difference of plastic deformation of crystal grain groups which are parallel to the rolling direction of the strip steel and have similar orientation, wherein the crystal grain groups are considered to be generated by solidification columnar crystals, phase transformation can not or rarely occur in the hot rolling and annealing processes, a strip-shaped structure is formed in a hot rolled plate, and finally the strip-shaped structure is remained on a cold-rolled annealed plate; therefore, the generation of wrinkles in the ferritic stainless steel is effectively inhibited by breaking the band-shaped structure in the hot-rolled sheet and inhibiting the formation of the aggregated structure on the cold-rolled annealed sheet.
In industrial production, generally, bell-type furnace annealing and re-rolling are adopted, wherein long-time heat preservation annealing is required, and researches show that the recrystallization rate increases along with the prolonging of the heat preservation time, but even a hot-rolled plate can still see obvious banded cluster structures after being preserved for 30 hours, and the plasticity and cold processing performance of the ferritic stainless steel are not greatly improved.
Patent CN104017971A proposes that the direction perpendicular to the hot rolling direction on the rolling surface of the hot rolled ferritic stainless steel plate (i.e. the transverse direction of the hot rolled annealed plate) is selected as the cold rolling direction during the cold rolling process, and annealing treatment is performed after the cold rolling to obtain the ferritic stainless steel plate with excellent anti-wrinkling performance.
Patent CN104294004A proposes a smelting method for increasing the equiaxial rate of 430 ferritic stainless steel ingots, which requires deoxidation to strictly control the extremely low oxygen content, controls the Al content in a certain range to form a certain amount of alumina inclusion, then adds silicon-magnesium alloy for casting, and finally forms silicon oxide-alumina-magnesium oxide inclusion with uniform components, wherein the impurity can be used as a solidification nucleation particle of ferritic stainless steel and has a certain number density, promotes the crystallization of the ferritic stainless steel in the solidification process to increase the equiaxial crystal rate, thereby achieving the effects of improving the structure and reducing wrinkling; the patent introduces that Al content and oxygen content need to be strictly controlled, ensures that inclusion composition meets requirements after magnesium treatment, also strictly requires that magnesium content is in 3-12 ppm during magnesium treatment, and too high or too low is unfavorable for ferrite stainless steel solidification nucleation, and the patent experiment process is complicated, and equipment, precision requirement are high, are unfavorable for large-scale production, have certain limitation.
Patent CN109536690A proposes a heat treatment process for a ferritic stainless steel rolled strip, which divides a banded structure in the rolled strip by reversible phase change and recrystallization, and the process is characterized in that the repeated heat treatment is carried out in a temperature interval of a ferrite phase and an austenite phase region after hot rolling, the cooling is carried out to 200-250 ℃ for air cooling, then a ferrite alpha phase and fine dispersed carbide are obtained, and then cold rolling annealing is carried out to obtain a sufficient recrystallization structure, thereby realizing the improvement of anti-wrinkling property and r value; the method has the advantages of longer heat preservation time in a double-phase region after hot rolling, repeated heat treatment, higher energy consumption and more complex implementation compared with the method.
Disclosure of Invention
The invention aims to provide a heat treatment method for improving phase-change ferrite stainless steel surface wrinkling, which is characterized in that heat treatment is carried out in a two-phase temperature area, martensite structures are generated in a dispersed manner through rapid cooling, the banded structures in a hot-rolled steel strip are broken through division, martensite is converted into ferrite in the cold rolling annealing process, crystal grains with different orientations from those of surrounding ferrite are formed, the formation of crystal grain clusters is avoided, the wrinkling phenomenon of stamping and stretching is reduced, the product quality is improved, and the production cost is saved.
The method of the invention is carried out according to the following steps:
1. smelting molten steel according to set components, and then preparing a continuous casting billet, wherein the components comprise, by mass, 0.03-0.13% of C, 0.2-1.2% of Si, 0.2-0.6% of Mn, less than or equal to 0.008% of S, less than or equal to 0.04% of P, less than or equal to 0.04% of N, 12.00-20.00% of Cr, and the balance of Fe and unavoidable impurities;
2. heating the casting blank to 1150-1250 ℃, preserving heat for 1-2 h, then carrying out hot rolling, wherein the initial rolling temperature is 980-1150 ℃, the final rolling temperature is 780-950 ℃, the total reduction rate is 60-95%, and air cooling to room temperature to obtain a hot rolled plate;
3. heating the hot rolled plate to 800-1150 ℃, then preserving heat for 10-60 min for annealing, and then performing water quenching to room temperature to obtain an annealed plate;
4. cold rolling the annealed sheet to obtain a cold-rolled sheet, wherein the total rolling reduction rate of the cold rolling is 80-95%;
5. and heating the cold-rolled sheet to 870-1080 ℃, preserving heat for 2-20 min, carrying out secondary annealing, and then air-cooling to room temperature to obtain the ferritic stainless steel plate.
In the step 2, the hot rolling pass is 6 to 8 passes.
In the step 2, the thickness of the hot-rolled plate is 1 to 8 mm.
In the step 4, the cold rolling process is divided into three sections, the rolling reduction of the first cold rolling pass is 4-20%, and 3 passes are carried out in total; the rolling reduction of the second stage cold rolling pass is 5-25%, and 5 passes are carried out in total; and the rolling reduction of the third cold rolling pass is 1-5%, and 2 passes are performed in total.
In the step 4, the thickness of the cold-rolled plate is 0.2-1.0 mm.
The tensile strength of the ferritic stainless steel sheet is 431.32-463.92 MPa.
The principle of the invention is as follows: heat-treating in a ferrite + austenite two-phase temperature region (800 to 1150 ℃), dispersing and generating a martensite structure in parent phase ferrite by a rapid cooling treatment (water quenching), applying a rolling force to the martensite structure and the ferrite structure during cold rolling, so that the martensite structure is harder than the ferrite structure, the ferrite structure of the adjacent martensite structure is subjected to large plastic deformation, the deformation is caused by uneven distribution of the martensite structure, and is a place where random recrystallization grain nucleation occurs, and the band structure in the hot-rolled steel strip is broken to develop a {111} structure, thereby suppressing the formation of a cohesive structure in the cold-rolled annealed steel strip; meanwhile, in the cold rolling annealing process, martensite is converted into ferrite to form crystal grains with different orientations with the surrounding ferrite, so that the formation of crystal grain clusters is avoided, the wrinkling phenomenon of the stainless steel in stamping and stretching is further reduced, the r value of austenite is improved, the product quality is improved, the production cost is saved, and the method is suitable for large-scale industrial production.
The heat treatment process can reduce the wrinkling phenomenon of the stainless steel in the processes of stamping and drawing, and improve the structure performance and the quality effect of the product of the ferritic stainless steel.
Drawings
FIG. 1 is a schematic view showing a hot rolled sheet annealing-cooling-cold rolling-secondary annealing process according to an embodiment of the present invention and a conventional method;
in the drawings, the upper diagram is an embodiment of the present invention, and the lower diagram is a conventional method;
FIG. 2 is a microstructure diagram of a hot-rolled sheet according to example 1 of the present invention;
FIG. 3 is a microstructure view of a ferritic stainless steel sheet according to example 1 of the present invention;
FIG. 4 is a microstructure view of an annealed plate according to example 1 of the present invention;
FIG. 5 is a microstructure view of a comparative annealed plate of a comparative experiment.
Detailed Description
The device used for observing the microstructure in the embodiment of the invention is a Zeiss LSM700 laser confocal microscope.
The standard adopted for wrinkling and stamping performance tests in the embodiment of the invention is GB2027-85 Experimental method for plastic strain ratio (r value) of sheet metal.
In the embodiment of the invention, the wrinkle resistance is evaluated by the wrinkle height Rmax after 15% stretching, the surface wrinkle height is measured by a laser confocal microscope, and the average plastic strain ratio can be used for the stamping property
And a lug parameter (Δ r).
In the embodiment of the invention, the calculation formula of the average plastic strain ratio is as follows:
in the formula (I), the compound is shown in the specification,
is the average plastic strain ratio, r0°For measuring the plastic strain ratio, r, after preparing a sample in a direction parallel to the rolling direction45°The plastic strain ratio, r, measured after the sample is prepared along the direction forming an included angle of 45 degrees with the rolling direction90°The plastic strain ratio is measured after a sample is prepared along the direction (vertical direction) which forms an included angle of 90 degrees with the rolling direction.
The calculation formula of the lug parameter in the embodiment of the invention is as follows:
where Δ r is the lobe parameter.
In the embodiment of the invention, the molten steel is smelted, refined and continuously cast into a continuous casting billet by adopting a blast furnace, an AOD converter, an LF refining furnace and a CCM continuous casting machine.
The corrugation height of the ferritic stainless steel plate in the embodiment of the invention is 6.28-9.61 mu m.
Example 1
Smelting molten steel according to set components, and then preparing a continuous casting billet, wherein the components comprise, by mass, 0.055% of C, 0.28% of Si, 0.33% of Mn, 0.001% of S, 0.021% of P, 0.025% of N, 16.59% of Cr, and the balance of Fe and inevitable impurities;
heating the casting blank to 1150 ℃, preserving heat for 2h, then carrying out 8-pass hot rolling, wherein the initial rolling temperature is 980 ℃, the final rolling temperature is 780 ℃, the total reduction rate is 95%, and air cooling to room temperature to obtain a hot rolled plate with the thickness of 2 mm; the microstructure of the hot-rolled plate is shown in FIG. 2;
the subsequent flow is shown in the upper diagram of FIG. 1;
heating the hot rolled plate to 950 ℃, then preserving heat for 20min for annealing, and then carrying out water quenching to room temperature to obtain an annealed plate; the microstructure is shown in FIG. 4;
cold rolling the annealed sheet to make the cold-rolled sheet, wherein the total reduction rate of the cold rolling is 85%; the cold rolling process is divided into three sections, the rolling reduction of the first section of cold rolling pass is 4-20%, and 3 passes are carried out in total; the rolling reduction of the second stage cold rolling pass is 5-25%, and 5 passes are carried out in total; the rolling reduction of the third cold rolling pass is 1-5%, and 2 passes are performed in total;
the thickness of the cold-rolled plate is 0.3 mm;
heating the cold-rolled sheet to 1000 ℃, preserving heat for 5min for secondary annealing, and then air-cooling to room temperature to obtain a ferritic stainless steel plate, wherein the tensile strength of the ferritic stainless steel plate is 445.56MPa, and the microstructure of the ferritic stainless steel plate is shown in figure 3;
the ferritic stainless steel plate is subjected to wrinkling and punching performance tests, wherein the wrinkling height is 8.05 mu m, the average plastic strain ratio is 1.36, and the lug parameter is 0.48;
performing a comparison test on hot rolled plates of the same material by adopting a traditional method, annealing the hot rolled plates, cooling the annealed plates to room temperature along with a furnace to obtain comparison annealed plates, and preparing a comparison ferritic stainless steel plate by the same steps and the flow shown in the lower graph of the figure 1; the microstructure of the comparative annealed plate is shown in FIG. 5;
performing wrinkling and punching performance tests on the comparative ferritic stainless steel plate, wherein the wrinkling height is 14.98 mu m, the average plastic strain ratio is 1.13, and the lug parameter is 0.44;
through the accelerated cooling of the annealing plate and the cooperation with other operations, the wrinkling defect of the ferritic stainless steel is effectively reduced, the processing performance of the stainless steel is improved, and the parameters of the lugs are basically unchanged.
Example 2
The method is the same as example 1, except that:
(1) the components of the continuous casting slab comprise, by mass, 0.039% of C, 0.45% of Si, 0.20% of Mn, 0.004% of S, 0.031% of P, 0.035% of N and 19.24% of Cr;
(2) heating the casting blank to 1250 ℃, preserving heat for 1h, then carrying out 7-pass hot rolling, wherein the initial rolling temperature is 1150 ℃, the final rolling temperature is 950 ℃, the total reduction rate is 80%, and air cooling to room temperature to obtain a hot rolled plate with the thickness of 3 mm;
(3) heating the hot rolled plate to an annealing temperature of 1050 ℃ for 25 min;
(4) the total reduction rate of cold rolling is 80 percent;
(5) the thickness of the cold-rolled plate is 0.6 mm;
(6) the secondary annealing temperature is 950 ℃, and the time is 20 min; the tensile strength of the ferritic stainless steel sheet is 431.32 MPa;
(7) ferritic stainless steel sheets and were subjected to ridging and punching performance tests, the ridging height was 6.28 μm, the average plastic strain ratio was 1.42, and the lug parameter was 0.50.
Example 3
The method is the same as example 1, except that:
(1) the components of the continuous casting billet comprise, by mass, 0.09% of C, 0.80% of Si, 0.58% of Mn, 0.007% of S, 0.035% of P, 0.03% of N and 13.2% of Cr;
(2) heating the casting blank to 1200 ℃, preserving heat for 1.5h, then carrying out 6-pass hot rolling, wherein the initial rolling temperature is 1050 ℃, the final rolling temperature is 850 ℃, the total reduction rate is 75%, and air cooling to room temperature to obtain a hot rolled plate with the thickness of 4 mm;
(3) heating the hot rolled plate to an annealing temperature of 1150 ℃ for 30 min;
(4) the total cold rolling reduction is 95 percent;
(5) the thickness of the cold-rolled plate is 0.2 mm;
(6) the secondary annealing temperature is 1000 ℃, and the time is 10 min; the tensile strength of the ferritic stainless steel sheet is 463.92 MPa;
(7) ferritic stainless steel sheets and were subjected to ridging and punching property tests, the ridging height was 9.61 μm, the average plastic strain ratio was 1.21, and the lug parameter was 0.46.
In examples 1, 2 and 3, martensite structures are generated after quenching, the martensite structure is more in example 3, the martensite structure is randomly distributed in the subsequent cold rolling, so that the peripheral ferrite structure has larger plastic deformation, the banded structure in the hot rolled steel is divided and destroyed, the formation of an aggregated structure is inhibited, annealing recrystallization is carried out after the cold rolling, the {111} texture is developed, and the wrinkling performance and the r value (plastic strain ratio) of the ferritic stainless steel are improved; in the comparative test, no martensite structure is generated after the hot rolled plate is annealed along with the furnace, the structure is mainly strip-shaped ferrite and is distributed in a layered manner, and simultaneously, carbides are dispersed and distributed, so that the cold processing performance is very unfavorable.
Claims (6)
1. A heat treatment method for improving the surface wrinkling of phase-change ferritic stainless steel is characterized by comprising the following steps:
(1) smelting molten steel according to set components, and then preparing a continuous casting billet, wherein the components comprise, by mass, 0.03-0.13% of C, 0.2-1.2% of Si, 0.2-0.6% of Mn, less than or equal to 0.008% of S, less than or equal to 0.04% of P, less than or equal to 0.04% of N, 12.00-20.00% of Cr, and the balance of Fe and unavoidable impurities;
(2) heating the casting blank to 1150-1250 ℃, preserving heat for 1-2 h, then carrying out hot rolling, wherein the initial rolling temperature is 980-1150 ℃, the final rolling temperature is 780-950 ℃, the total reduction rate is 60-95%, and air cooling to room temperature to obtain a hot rolled plate;
(3) heating the hot rolled plate to 800-1150 ℃, then preserving heat for 10-60 min for annealing, and then performing water quenching to room temperature to obtain an annealed plate;
(4) cold rolling the annealed sheet to obtain a cold-rolled sheet, wherein the total cold rolling reduction rate is 80-95%;
(5) and heating the cold-rolled sheet to 870-1080 ℃, preserving heat for 2-20 min, carrying out secondary annealing, and then air-cooling to room temperature to obtain the ferritic stainless steel plate.
2. The heat treatment method for improving the surface wrinkling of the phase-change ferritic stainless steel according to claim 1, characterized in that in the step (2), the hot rolling pass is 6-8 passes.
3. The heat treatment method for improving surface wrinkling of phase-change ferritic stainless steel according to claim 1, characterized in that in step (2), the thickness of the hot-rolled sheet is 1 to 8 mm.
4. The heat treatment method for improving the surface wrinkling of the phase-change ferritic stainless steel according to claim 1, characterized in that in the step (4), the cold rolling process is divided into three sections, the reduction rate of the first cold rolling pass is 4-20%, and 3 passes are performed in total; the rolling reduction of the second stage cold rolling pass is 5-25%, and 5 passes are carried out in total; and the rolling reduction of the third cold rolling pass is 1-5%, and 2 passes are performed in total.
5. The heat treatment method for improving the surface wrinkling of the phase-change ferritic stainless steel according to claim 1, characterized in that in the step (4), the cold-rolled plate has a thickness of 0.2 to 1.0 mm.
6. The heat treatment method for improving the surface wrinkling of the phase-change ferritic stainless steel sheet according to claim 1, wherein the tensile strength of the ferritic stainless steel sheet is 431.32-463.92 MPa.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115044826A (en) * | 2022-05-07 | 2022-09-13 | 广西柳州钢铁集团有限公司 | 410 ferritic stainless steel |
| CN116479340A (en) * | 2023-04-28 | 2023-07-25 | 浙江丰业集团有限公司 | High-toughness ferritic steel pipe and preparation method thereof |
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| CN101748255A (en) * | 2008-11-28 | 2010-06-23 | 宝山钢铁股份有限公司 | Method for improving forming performance of 430 ferrite stainless strip steel |
| CN101649418A (en) * | 2009-09-10 | 2010-02-17 | 山西太钢不锈钢股份有限公司 | Ferrite stainless steel cold-rolled steel band and manufacturing method thereof |
| CN102534409A (en) * | 2012-02-08 | 2012-07-04 | 河北联合大学 | Anti-wrinkle ferritic stainless steel with low cost and production method thereof |
| CN104017971A (en) * | 2014-06-20 | 2014-09-03 | 北京科技大学 | Transverse cold rolling method for improving surface wrinkling of ferritic stainless steel |
| CN105331899A (en) * | 2015-09-24 | 2016-02-17 | 宝钢不锈钢有限公司 | Ferritic stainless steel with good crease resistance and manufacturing method of ferritic stainless steel |
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| CN115044826A (en) * | 2022-05-07 | 2022-09-13 | 广西柳州钢铁集团有限公司 | 410 ferritic stainless steel |
| CN115044826B (en) * | 2022-05-07 | 2023-09-15 | 广西柳州钢铁集团有限公司 | 410 ferrite stainless steel |
| CN116479340A (en) * | 2023-04-28 | 2023-07-25 | 浙江丰业集团有限公司 | High-toughness ferritic steel pipe and preparation method thereof |
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