CN114934164B - Method for improving favorable texture proportion of high-grade non-oriented silicon steel - Google Patents
Method for improving favorable texture proportion of high-grade non-oriented silicon steel Download PDFInfo
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- 238000000034 method Methods 0.000 title claims abstract description 43
- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 37
- 230000002349 favourable effect Effects 0.000 title claims abstract description 20
- 230000008569 process Effects 0.000 claims abstract description 20
- 229910052718 tin Inorganic materials 0.000 claims abstract description 8
- 238000003723 Smelting Methods 0.000 claims abstract description 5
- 230000009467 reduction Effects 0.000 claims description 21
- 238000000137 annealing Methods 0.000 claims description 17
- 238000005097 cold rolling Methods 0.000 claims description 13
- 229910000831 Steel Inorganic materials 0.000 claims description 11
- 239000010959 steel Substances 0.000 claims description 11
- 238000005096 rolling process Methods 0.000 claims description 10
- 238000005266 casting Methods 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 4
- 238000003756 stirring Methods 0.000 claims description 4
- 230000006698 induction Effects 0.000 abstract description 13
- 238000004519 manufacturing process Methods 0.000 abstract description 12
- 230000002829 reductive effect Effects 0.000 abstract description 7
- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 abstract description 4
- 230000002411 adverse Effects 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 238000005204 segregation Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000000126 substance Substances 0.000 description 6
- 238000010899 nucleation Methods 0.000 description 5
- 230000006911 nucleation Effects 0.000 description 5
- 238000009749 continuous casting Methods 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 238000004220 aggregation Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 238000004134 energy conservation Methods 0.000 description 2
- 238000007667 floating Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 239000000839 emulsion Substances 0.000 description 1
- 238000004146 energy storage Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 230000000638 stimulation Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000001360 synchronised effect Effects 0.000 description 1
- 230000003313 weakening effect Effects 0.000 description 1
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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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
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- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C—CHEMISTRY; METALLURGY
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/125—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with application of tension
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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Abstract
The invention relates to a method for improving the favorable texture proportion of high-grade non-oriented silicon steel, which comprises the following steps of adding 0.045-0.100% of Sn or Sb in percentage by weight in the smelting process, and controlling [ Mn ]/[ S ]: 200-400, [ Al ]/[ N ]:250 to 500 percent, ti is less than or equal to 0.0015 percent, and C is less than or equal to 0.0025 percent; meanwhile, the high-grade cold-rolled non-oriented electrical steel is produced by matching with the control of the production process, so that the {111} adverse texture components are effectively reduced, the favorable texture ratio is increased by more than 0.65%, and the high-frequency magnetic induction strength in the product is increased by more than 0.015T.
Description
Technical Field
The invention relates to the technical field of non-oriented silicon steel manufacturing, in particular to a method for improving the favorable texture proportion of high-grade non-oriented silicon steel.
Background
The non-oriented silicon steel product is widely applied to manufacturing of high-precision and sharp motors and instrument and meter iron cores, and is an important metal functional soft magnetic material. In the situation that energy conservation and emission reduction are advocated by the nation, the motor is used as main equipment of power consumption, and the reduction of the self loss and the improvement of the working efficiency are very important for energy conservation, so that the silicon steel material for manufacturing the motor iron core is required to have the performance of low iron loss and high magnetic induction. At present, the working frequency of the high-efficiency motor is changed from 50Hz or 60Hz which is originally fixed to a range of 10-1 kHz (the general frequency range is 400-1 kHz), so that the power consumption is low and the efficiency is high. However, as the frequency of use increases, the magnetic induction tends to decrease, and the influence of the process and texture on the magnetic induction is very remarkable. Meanwhile, the iron loss and the magnetic induction of the non-oriented silicon steel are synchronous, namely, the iron loss is reduced, and the magnetic induction is also reduced, so that the process adjustment can be carried out only in a certain range. For non-oriented silicon steel, the {100} and {110} textures are textures favorable for electromagnetic performance, while the {111} <112> textures on gamma-oriented lines are unfavorable, inhibiting the unfavorable textures, and increasing the duty ratio of the favorable textures is one of effective technical means for increasing magnetic induction.
The Chinese patent application with the application number 201911400226.X discloses a method for improving the eta texture occupancy rate in an ultra-thin strip of oriented silicon steel, wherein a commercial oriented silicon steel sheet with a conventional thickness and a thick specification and without a bottom layer or with a bottom layer is selected as a raw material, and the eta texture occupancy rate in the ultra-thin strip of the oriented silicon steel is improved by controlling strip steel tension, emulsion flow and an annealing process, but the method is not suitable for non-oriented silicon steel.
The Chinese patent application No. 201610288421.8 discloses a method for evaluating the magnetic performance of non-oriented silicon steel through texture indexes, and the quality of the texture can be accurately evaluated through the calculation of the texture indexes, so that the magnetic performance of the non-oriented silicon steel is analyzed. However, the method only provides a judging method for the performance quality of the non-oriented silicon steel, and does not relate to a method for obtaining favorable texture.
The Chinese patent application No. 201110133681.5 discloses a method for promoting the growth of GOSS textures of a silicon steel strip by using pulse current, which mainly aims at cold rolled silicon steel strips with the thickness of 0.1-0.5mm and the width of 10-150mm, pulse current is led into a moving silicon steel strip power-on region section by using a pulse power supply through a pair of electric contact devices, and the power-on region section of the silicon steel strip is continuously subjected to electric stimulation treatment in an air atmosphere, so that a large amount of GOSS textures are generated in the primary recrystallization process. Although the production cost is low, the technology is not suitable for industrial mass production.
The Chinese patent application No. 201710402813.7 discloses a method for preparing developed {100} plane texture non-oriented silicon steel thin strip based on thin strip continuous casting, which mainly aims at component and process design of non-oriented silicon steel produced by thin strip continuous casting, and the thickness of the cast strip after continuous casting is 1.5-2.0 mm. Although the effect is obvious, the technology is not suitable for the industrialized mass production of continuous casting thick slabs.
The Chinese patent application No. 201410531701.8 discloses a method for preparing high magnetic induction non-oriented electrical steel by utilizing columnar crystals, wherein a columnar crystal part is cut off from a square ingot with the silicon content of 6.0% -6.5%, hot rolling, pickling, warm rolling, intermediate annealing, cold rolling and final annealing are carried out along the normal direction of the columnar crystals to prepare the non-oriented silicon steel, a slab before hot rolling has columnar crystal structure with <001> preferred orientation, and the high magnetic induction non-oriented silicon steel is prepared by utilizing the hereditary property of {100} texture. Although the technology has obvious effect, the industrial mass production process is difficult to control.
Disclosure of Invention
The invention provides a method for improving the favorable texture proportion of high-grade non-oriented silicon steel, and the high-grade cold-rolled non-oriented electrical steel produced by the method effectively reduces the {111} unfavorable texture components, improves the favorable texture proportion by more than 0.65%, and improves the high-frequency magnetic induction strength in the product by more than 0.015T.
In order to achieve the above purpose, the invention is realized by adopting the following technical scheme:
a method for improving the favorable texture proportion of high-grade non-oriented silicon steel comprises the following steps:
1) 0.045-0.100% of Sn or Sb is added in the smelting process according to the weight percentage, and [ Mn ]/[ S ] is controlled: 200-400, [ Al ]/[ N ]:250 to 500 percent, ti is less than or equal to 0.0015 percent, and C is less than or equal to 0.0025 percent;
2) Near liquidus casting, the superheat degree is less than or equal to 15 ℃, the initial pulling speed is 0.3-0.5 m/min, the initial pulling speed is slowly increased at a speed of 0.02-0.10 m/min, and the stable pulling speed is 0.8-1.3 m/min; electromagnetic stirring is adopted in the casting process, and the current is more than or equal to 400A;
3) The hot rolling heating temperature is 1100-1200 ℃, the rough rolling R1 adopts large reduction, and the reduction rate is more than or equal to 30%; the final rolling temperature is 860-900 ℃ and the curling temperature is 680-750 ℃;
4) The normalizing temperature is 920-980 ℃, and the temperature is kept for 2-5 min;
5) The temperature of the strip steel before cold rolling is more than or equal to 50 ℃, and the first pass reduction rate after more than 5 passes of cold rolling meets the following conditions: a% = (0.25 to 0.35) d, wherein: a% -cold rolling first pass reduction rate; d-normalizing the average grain size of the plate in μm; the reduction rate of the final pass is more than or equal to 30 percent;
6) The belt steel tension in the annealing furnace is 2-4 kN, the annealing process speed is 75-90 m/min, and the annealing temperature meets the following conditions:
850+ (1000-1500) (Si+Al+Sn) T.ltoreq.900+ (1000-1500) (Si+Al+Sn) or
850+(1000～1500)(Si+Al+Sb)≤T≤900+(1000～1500)(Si+Al+Sb)。
In the non-oriented silicon steel, the weight percentage of Si+Al is more than 3.5 percent.
Compared with the prior art, the invention has the beneficial effects that:
1) The high-grade cold-rolled non-oriented electrical steel produced by the method effectively reduces the {111} adverse texture components, improves the favorable texture ratio by more than 0.65%, and improves the high-frequency magnetic induction strength in the product by more than 0.015T;
2) Sn and Sb elements are added into chemical components of the non-oriented silicon steel, are typical grain boundary segregation elements, are easy to selectively segregate near grain boundaries, and reduce grain boundary energy, and the driving force of grain growth is the grain boundary energy, so that grain boundary segregation of the elements can inhibit nucleation and growth of certain grains; the {111} oriented crystal grains are easy to form nuclei at the crystal boundary in the hot rolling and annealing processes, so that the nucleation and growth of the {111} oriented crystal grains near the crystal boundary are directly hindered by the segregation of Sn and Sb at the crystal boundary, the strength of {111} texture components in the finished strip steel is reduced, and the magnetic performance of the non-oriented silicon steel can be improved by reducing the proportion of {111} surface textures;
3) The ratio of Mn and S is limited to ensure good hot workability and coarsen MnS, and the ratio of Al and N is limited to facilitate the floating of inclusions and the aggregation coarsening of AlN in the later working procedure, so that {100}, {110} components are increased, and {111} components are weakened, thereby improving the magnetic performance; and the control of the production process is matched, so that the effect of improving the proportion of the favorable texture is finally realized.
Detailed Description
The invention discloses a method for improving the favorable texture proportion of high-grade non-oriented silicon steel, which comprises the following steps:
1) 0.045-0.100% of Sn or Sb is added in the smelting process according to the weight percentage, and [ Mn ]/[ S ] is controlled: 200-400, [ Al ]/[ N ]:250 to 500 percent, ti is less than or equal to 0.0015 percent, and C is less than or equal to 0.0025 percent;
2) Near liquidus casting, the superheat degree is less than or equal to 15 ℃, the initial pulling speed is 0.3-0.5 m/min, the initial pulling speed is slowly increased at a speed of 0.02-0.10 m/min, and the stable pulling speed is 0.8-1.3 m/min; electromagnetic stirring is adopted in the casting process, and the current is more than or equal to 400A;
3) The hot rolling heating temperature is 1100-1200 ℃, the rough rolling R1 adopts large reduction, and the reduction rate is more than or equal to 30%; the final rolling temperature is 860-900 ℃ and the curling temperature is 680-750 ℃;
4) The normalizing temperature is 920-980 ℃, and the temperature is kept for 2-5 min;
5) The temperature of the strip steel before cold rolling is more than or equal to 50 ℃, and the first pass reduction rate after more than 5 passes of cold rolling meets the following conditions: a% = (0.25 to 0.35) d, wherein: a% -cold rolling first pass reduction rate; d-normalizing the average grain size of the plate in μm; the reduction rate of the final pass is more than or equal to 30 percent;
6) The belt steel tension in the annealing furnace is 2-4 kN, the annealing process speed is 75-90 m/min, and the annealing temperature meets the following conditions:
850+ (1000-1500) (Si+Al+Sn) T.ltoreq.900+ (1000-1500) (Si+Al+Sn) or
850+(1000～1500)(Si+Al+Sb)≤T≤900+(1000～1500)(Si+Al+Sb)。
In the non-oriented silicon steel, the weight percentage of Si+Al is more than 3.5 percent.
The invention is suitable for the production of cold-rolled non-oriented silicon steel products with the (Si+Al) content of more than 3.5 percent, and the {100} component is reinforced and the {111} component is weakened by adjusting chemical components and improving the manufacturing process, so that the magnetic induction is improved.
The invention relates to a method for improving the favorable texture proportion of high-grade non-oriented silicon steel, which comprises the following chemical components and technical process design principles:
1. 0.045% -0.100% of Sn or Sb is added in the smelting process, and [ Mn ]/[ S ] is controlled: 200-400, [ Al ]/[ N ]:250 to 500 percent, ti is less than or equal to 0.0015 percent, and C is less than or equal to 0.0025 percent; sn and Sb elements are added into the chemical components, and are typical grain boundary segregation elements, so that the elements are easy to selectively segregate near grain boundaries, the grain boundary energy is reduced, and the driving force for grain growth is the grain boundary energy, so that the grain boundary segregation of the elements can inhibit nucleation and growth of certain grains. The {111} oriented crystal grains are easy to form nuclei at the crystal boundary in the hot rolling and annealing processes, so that the nucleation and growth of the {111} oriented crystal grains near the crystal boundary are directly hindered by the segregation of Sn and Sb at the crystal boundary, the strength of {111} texture components in the finished strip steel is reduced, the proportion of {111} surface textures is reduced, and the magnetic performance of the non-oriented silicon steel can be improved; controlling the ratio of Mn to S ensures good hot workability and coarsens MnS; the control of the ratio of Al to N is favorable for the floating of the inclusions and the aggregation coarsening of AlN in the subsequent working procedure, and promotes the increase of {100}, {110} components and the weakening of {111} components, thereby improving the magnetic performance. And then the matched technological process control is combined, and finally the effect of improving the favorable texture ratio is realized.
2. Near liquidus casting, controlling the superheat degree to be less than or equal to 15 ℃, controlling the initial pulling speed to be 0.3-0.5 m/min, slowly rising at the speed of 0.02-0.10 m/min, stabilizing the pulling speed to be 0.8-1.3 m/min, and carrying out electromagnetic stirring in the casting process, wherein the current is more than or equal to 400A, so that the equiaxial crystal proportion can be improved.
3. The heating temperature is 1100-1200 ℃, rough rolling R1 adopts large reduction, the reduction rate is more than or equal to 30%, and the original columnar crystal structure is favorably destroyed, and specific crystal structure and texture components are obtained; the final rolling temperature is 860-900 ℃ and the curling temperature is 680-750 ℃.
3. The normalizing temperature is 920-980 ℃, the temperature is kept for 2-5 min, the segregation of the meta-polymerized element at the grain boundary is ensured, and the adverse texture components are inhibited.
4. The temperature of the strip steel before cold rolling is more than or equal to 50 ℃, and after 5-pass cold rolling, the first-pass reduction ratio meets the following conditions: a% = (0.25-0.35) d, ensures stable and smooth running of the cold rolling process, and the reduction rate of the last pass is more than or equal to 30%. The stronger {001} <110> texture is retained over a larger thickness of the surface region after rolling is completed, thereby limiting the annealed {111} <112> texture over a larger range.
5. The belt steel tension in the annealing furnace is 2-4 kN, the annealing process speed is 75-90 m/min, and the annealing temperature meets the following conditions:
850+ (1000-1500) (Si+Al+Sn) T.ltoreq.900+ (1000-1500) (Si+Al+Sn) or
850+(1000～1500)(Si+Al+Sb)≤T≤900+(1000～1500)(Si+Al+Sb)。
The original energy storage form of each grain orientation of the cold-rolled steel strip is changed through tension control, so that the components with favorable textures are nucleated preferentially; through the adjustment of the technical process, the nucleation and growth time of recrystallized grains is increased, the purpose of homogenizing the grains is achieved, and finally the electromagnetic performance is improved.
The following examples are given by way of illustration of detailed embodiments and specific procedures based on the technical scheme of the present invention, but the scope of the present invention is not limited to the following examples.
[ example ]
The main chemical compositions of the non-oriented silicon steel in examples 1-3 are shown in Table 1; the production process parameters are shown in Table 2; the effect of the implementation is shown in Table 3.
TABLE 1 Main chemical Components (wt%)
| Composition of the components | C | Si+Al | Mn/S | Al/N | Ti | Sn | Sb |
| Example 1 | 0.0022 | 4.08 | 300 | 410 | 0.0009 | 0.05 | — |
| Example 2 | 0.0021 | 3.95 | 280 | 430 | 0.0010 | — | 0.065 |
| Example 3 | 0.0024 | 3.58 | 370 | 300 | 0.0012 | 0.06 | — |
TABLE 2 main process parameters
TABLE 3 effect of implementation
| The improvement ratio of the favorable texture proportion is percent | Magnetic induction intensity enhancement value, T | |
| Example 1 | 0.90 | 0.021 |
| Example 2 | 0.65 | 0.018 |
| Example 3 | 0.69 | 0.015 |
The foregoing is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art, who is within the scope of the present invention, should make equivalent substitutions or modifications according to the technical scheme of the present invention and the inventive concept thereof, and should be covered by the scope of the present invention.
Claims (1)
1. The method for improving the favorable texture proportion of the high-grade non-oriented silicon steel is characterized by comprising the following steps of:
1) In the non-oriented silicon steel, si+Al is more than 3.5 percent by weight; 0.045-0.100% of Sn or Sb is added in the smelting process according to the weight percentage, and [ Mn ]/[ S ] is controlled: 200-280, [ Al ]/[ N ]:250 to 300 percent, 0.0009 to 0.1112 percent of Ti, and less than or equal to 0.0025 percent of C;
2) Near liquidus casting, the superheat degree is less than or equal to 15 ℃, the initial pulling speed is 0.3-0.5 m/min, the initial pulling speed is slowly increased at a speed of 0.02-0.10 m/min, and the stable pulling speed is 0.8-1.3 m/min; electromagnetic stirring is adopted in the casting process, and the current is more than or equal to 400A;
3) The hot rolling heating temperature is 1130-1200 ℃, rough rolling R1 adopts large reduction, and the reduction rate is more than or equal to 30%; the final rolling temperature is 860-900 ℃ and the curling temperature is 680-750 ℃;
4) The normalizing temperature is 970-980 ℃, and the temperature is kept for 2-5 min;
5) The temperature of the strip steel before cold rolling is more than or equal to 50 ℃, and the first pass reduction rate after more than 5 passes of cold rolling meets the following conditions:
wherein: a% -cold rolling first pass reduction rate; d-normalizing the average grain size of the plate in μm; the reduction rate of the final pass is more than or equal to 30 percent;
6) The belt steel tension in the annealing furnace is 2-4 kN, the annealing process speed is 75-90 m/min, and the annealing temperature meets the following conditions:
or (b)。
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