CN110592351A - Production process of high magnetic induction oriented steel - Google Patents
Production process of high magnetic induction oriented steel Download PDFInfo
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- CN110592351A CN110592351A CN201911055531.XA CN201911055531A CN110592351A CN 110592351 A CN110592351 A CN 110592351A CN 201911055531 A CN201911055531 A CN 201911055531A CN 110592351 A CN110592351 A CN 110592351A
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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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- 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
- C21D8/1233—Cold rolling
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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
- C21D8/1244—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
- C21D8/1255—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 diffusion of elements, e.g. decarburising, nitriding
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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
- C21D8/1244—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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- 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
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1283—Application of a separating or insulating coating
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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
- C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
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- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
The invention relates to the field of steel processing, and particularly discloses a production process of high magnetic induction oriented steel, which comprises the steps of silicon steel continuous casting slab processing; rough rolling and finish rolling of the silicon steel continuous casting plate blank; a two-stage normalizing step; cold rolling; a decarburization annealing step; a nitriding processing step; an annealing release agent coating step; a high-temperature annealing step; an insulating coating film and a stretch annealing step; and (3) laser scoring. Before cold rolling processing is carried out on the steel plate, rough rolling, finish rolling and normalizing processing, acid pickling dephosphorization and edge shearing are carried out on the steel plate, and during cold rolling processing, the surface of the steel plate is not easy to have the accidents of edge cracking and fracture, so that the cold rolling efficiency of the steel plate can be improved.
Description
Technical Field
The invention belongs to the field of steel processing, and particularly relates to a production process of high-magnetic-induction oriented steel.
Background
10 new steel materials including high-performance silicon steel are the key points of the development of China in the next three years, and meet the industrial policy of China and the requirement of upgrading and updating of the transformer industry, high-magnetic induction oriented electrical steel in the high-performance silicon steel is a necessary material required in the power industry, and the development of the power industry is determined by the performance and updating of the high-magnetic induction oriented electrical steel.
In the production process of the high magnetic induction oriented electrical steel, the steel plate is limited by the reduction rate in cold rolling, and when the reduction rate is too low, the cold rolling efficiency of the steel plate can be greatly influenced, and the processing efficiency of the high magnetic induction oriented electrical steel is influenced; however, when the reduction ratio is too high, the accidents of edge cracking and fracture often occur, the strip steel layer and the strip steel layer are easy to adhere, the production efficiency is affected, a large amount of iron loss is caused, the magnetic performance of the oriented silicon steel is not high, and the production cost of the high-magnetic-induction oriented electrical steel is increased.
Disclosure of Invention
The invention aims to provide a production process of high magnetic induction oriented steel capable of improving the cold rolling efficiency of a steel plate so as to improve the processing efficiency of the high magnetic induction oriented steel and reduce the iron loss of the high magnetic induction oriented steel.
In order to achieve the above object, the basic scheme of the invention is as follows: the production process of the high magnetic induction oriented steel comprises the following steps:
step 1: preparing steel for steelmaking, and carrying out steelmaking on the steel by adopting a converter or an electric furnace to obtain molten steel; carrying out vacuum degassing treatment on the molten steel to obtain a silicon steel continuous casting slab;
step 2: heating the silicon steel continuous casting slab at the temperature of 1150-1300 ℃ to enable the temperature of the silicon steel continuous casting slab to reach 1150-1300 ℃, then carrying out rough rolling on the silicon steel continuous casting slab to 40-70mm, and then carrying out fine rolling on the silicon steel continuous casting slab, wherein the cumulative reduction rate of the fine rolling is more than 90%;
and step 3: after the finish rolling, rapidly cooling the hot-rolled silicon steel plate, and then coiling the steel plate, wherein the temperature of the coiled steel plate is below 600 ℃;
and 4, step 4: normalizing the steel plate by adopting two-stage normalization;
and 5: performing cold rolling processing on the normalized steel plate, wherein the final reduction rate of the cold rolling is more than 80%, and the temperature of the steel plate is kept at 190-210 ℃ during the cold rolling;
step 6: introducing the cold-rolled steel plate into a continuous annealing furnace for decarburization annealing, heating the steel plate to 770-900 ℃, and adopting a protective atmosphere, wherein the oxidation degree (PH2O/PH2) of the protective atmosphere is 0.35-0.45, the concentration of carbon element is less than or equal to 25ppm, and the concentration of oxygen element is 600-700 ppm;
and 7: after decarburization annealing, introducing ammonia gas with higher nitriding energy into the independent furnace section of the annealing furnace in the step 6, so that the ratio of the nitrogen element content in the steel plate to the aluminum element content in the steel plate is more than 2: 4;
and 8: coating an annealing release agent on the surface of the steel plate subjected to the nitriding treatment in the step 7;
and step 9: annealing the steel plate at high temperature to generate recrystallized grains with the orientation of {110} <100 >;
step 10: coating an insulating coating film on the surface of the steel plate subjected to high-temperature annealing, and then performing stretching annealing;
step 11: and carrying out laser scoring on the steel plate after the stretching annealing.
The principle and advantages of the basic scheme are as follows: before the cold rolling in the step 3, the steel plate is subjected to rough rolling, finish rolling and normalizing, the cold rolling difficulty and strength during the cold rolling can be reduced after the rough rolling and the finish rolling, and meanwhile, after the finish rolling is adopted, the thickness of the silicon steel continuous casting plate blank is reduced, the silicon steel continuous casting plate blank can be cooled in time, the steel plate cannot be recrystallized, and the improvement of magnetic induction is facilitated; meanwhile, the surface tension of the steel plate is improved after normalization, and the surface of the steel plate is not easy to have the accidents of edge cracking and fracture during cold rolling processing; under the technical guarantee, when the temperature of the steel plate is kept at 190-210 ℃ during cold rolling processing in the step 5, the toughness of the steel plate is further improved, and the final reduction rate of the cold rolling is controlled to be more than 80 percent, so that the surface of the steel plate can not be cracked or broken, and the iron loss is reduced; and the processing efficiency of cold rolling can be improved, and the processing efficiency of the whole steel plate is improved.
Meanwhile, after the steel plate is annealed in the step 6, crystal grains in the steel plate can be refined, deformation and cracks on the steel plate can be further reduced, and meanwhile, the quality of nitrogen and aluminum in the steel plate is controlled in the step 7, so that the content of the nitrogen can be effectively controlled, and the processed high-magnetic-induction oriented electrical steel has the characteristics of wear resistance, fatigue resistance, corrosion resistance and high-temperature resistance.
Step 8 and step 9, by coating the annealing separant, recrystallized grains with the {110} <100> orientation can be effectively formed in the steel plate, the grains in the steel plate are further refined, the wear resistance, fatigue resistance, corrosion resistance and high temperature resistance of the steel plate are further improved, the preparation for the stretching annealing in the step 10 is also facilitated, and the accidents of edge cracking and fracture of the steel plate in the stretching annealing process are avoided.
Further, in step 2, the reduction ratio of the final pass of the finish rolling is 25% or more.
On the basis of processing the silicon steel continuous casting slab by rough rolling, the single reduction rate is higher during finish rolling, the number of finish rolling times can be reduced, and the processing efficiency of the whole rolling process is improved.
Further, in step 2, the reduction ratio of the final pass of the finish rolling is 30% or more.
When the reduction ratio of the final pass of the finish rolling is 30% or more, the processing efficiency of the rolling is further improved.
Further, in the step 4, when the steel plate is normalized by adopting two-stage normalization, in the first stage of heating normalization, the temperature rise speed is 5-10 ℃/s, when the temperature rises to more than 1100 ℃, the temperature is kept for 30 seconds, and then the temperature is immediately reduced; in the second stage of heating and normalizing, the annealing speed is more than or equal to 6 ℃/s, the crystal grain structure in the steel plate keeps the lamellar interval, and the cooling speed is 50 ℃/s.
By adopting multi-section normalizing processing, the dephosphorization of the steel plate can be more thorough, the subsequent cold rolling processing is more convenient, the grain structure in the steel plate keeps the layered interval, the steel plate can be extended in the horizontal direction when the subsequent cold rolling processing is convenient, and the risk of edge cracking and fracture is reduced.
Further, the grain structure in the steel sheet maintains a lamellar spacing, and the lamellar spacing reaches 20 μm.
The layered interval reaches a better state suitable for cold rolling, and is convenient for cold rolling processing.
Further, in step 7, after the nitriding treatment, the ratio of the nitrogen element content in the steel sheet to the aluminum element content in the steel sheet is greater than 2: 3.
The concentration of the carbon element in the protective atmosphere is far lower than that of the oxygen element, so that the oxygen element can quickly consume the carbon element in the steel plate when decarburization annealing is guaranteed, the decarburization efficiency is effectively improved, and meanwhile the carbon element in the protective atmosphere can be prevented from entering the steel plate.
Further, in step 10, the thickness of the insulating coating film is set so that the coating amount becomes 4.0 to 5.0g/m2。
The coating amount of the insulating coating film can ensure that the surface tension on the surface of the steel plate is increased, and the iron loss is reduced.
Further, in step 10, the thickness of the insulating coating film is such that the coating amount becomes 4.5g/m2。
Insulating coating film 4.5g/m2The coating amount of (2) can ensure that the tension on the surface of the steel plate is increased, and the waste of redundant insulating coating films is avoided.
Further, in step 5, the temperature of the steel sheet at the time of cold rolling was maintained at 195-.
The toughness of the steel plate is improved from the temperature, and the phenomena of edge cracking and fracture can not occur in cold rolling processing.
Further, in step 8, the annealing separator is MgO annealing separator or TiO2 annealing separator.
The use of the MgO annealing separator can enhance the annealing separation effect of the annealing separator.
Drawings
FIG. 1 is a schematic front view of a coating apparatus according to example 2 of the present invention;
FIG. 2 is an enlarged cross-sectional view of the coating mechanism of FIG. 1;
fig. 3 is a top view of the winding mechanism in fig. 1.
Detailed Description
The following is further detailed by the specific embodiments:
reference numerals in the drawings of the specification include: the device comprises a conveyor belt 10, a rectangular limit frame 101, a containing box 20, a flow guide pipe 201, a coating block 202, a coating hole 203, a flow guide cavity 204, a communication hole 205, a sponge 206, a support column 30, a reel 401, a support bearing 402, a spring rod 403, a pressure spring 404, a fixing plate 405 and a steel plate 60.
Example 1
The embodiment 1 includes a production process of high magnetic induction oriented steel, and specifically includes the following steps:
step 1: preparing steel for steelmaking, and carrying out steelmaking on the steel by adopting a converter or an electric furnace to obtain molten steel; carrying out vacuum degassing treatment on the molten steel, and then casting to obtain a silicon steel continuous casting slab;
step 2: heating the continuous silicon steel cast slab at the temperature of 1150-1300 ℃ to enable the temperature of the continuous silicon steel cast slab to reach 1150-1300 ℃, then carrying out rough rolling on the continuous silicon steel cast slab to 40-70mm, then carrying out fine rolling on the continuous silicon steel cast slab, wherein the accumulated reduction rate of the fine rolling is over 90 percent, and the reduction rate of the final pass of the fine rolling is over 30 percent;
and step 3: after the finish rolling, cooling the silicon steel continuous casting plate blank to form a steel plate, and then coiling the steel plate, wherein the temperature of the coiled steel plate is below 600 ℃;
and 4, step 4: normalizing the steel plate by adopting two-stage normalization, wherein in the first stage of heating normalization, the temperature rise speed is 5-10 ℃/s, when the temperature rises to more than 1100 ℃, the temperature is kept for 30 seconds, and then the temperature is immediately reduced; in the second stage of heating and normalizing, the annealing speed is more than or equal to 6 ℃/s, the crystal grain structure in the steel plate keeps the lamellar interval, the lamellar interval reaches 20 mu m, and the cooling speed is 50 ℃/s; then carrying out shot blasting treatment on the steel plate; then, carrying out acid cleaning on the steel plate, carrying out acid cleaning by adopting a sulfuric acid aqueous solution, and carrying out edge cutting treatment on the edge of the steel plate during acid cleaning processing;
and 5: performing cold rolling processing on the steel plate after the acid washing, wherein the final reduction rate of the cold rolling is more than 80%, and the temperature of the steel plate is kept at 195-205 ℃ during the cold rolling;
step 6: placing the cold-rolled steel plate into an annealing device for decarburization annealing, adopting a protective atmosphere when the steel plate is heated to 770-900 ℃, and enabling the oxidation degree of the protective atmosphere (PH2O/PH2) to be less than or equal to 25ppm and the concentration of oxygen to be 600-700 ppm;
and 7: after decarburization annealing, filling nitrided ammonia gas into the annealing device in the step 4 to ensure that the ratio of the nitrogen element content in the steel plate to the aluminum element content in the steel plate is more than 2: 3;
and 8: coating an annealing release agent on the surface of the steel plate subjected to the nitriding treatment in the step 5, wherein the annealing release agent is an MgO annealing release agent;
and step 9: annealing the steel plate at high temperature to generate recrystallized grains with the orientation of {110} <100 >;
step 10: coating an insulating coating film on the surface of the steel sheet after high-temperature annealing to a thickness of 4.5g/m2Then carrying out stretching annealing;
step 11: and carrying out laser scoring on the steel plate after the stretching annealing.
After the process is used, the high magnetic induction oriented steel produced by the process is detected, medium-sized coils of Hi-B steel with the specification of 0.27mm are subjected to decarburization and N penetration tests, and N penetration parameters of all positions at the head and the tail of a single coil of the high magnetic induction oriented steel are respectively measured during the detection, so that the test results in table 1 are obtained.
TABLE 1
As is clear from the data in Table 1, the amount of N penetration substantially reached the target value, and the C content after decarburization was less than 25ppm, which was acceptable.
Meanwhile, after the steel coil is treated according to a preset high-temperature annealing process, and then is coated with an insulating coating and subjected to stretching annealing, the iron loss condition of the three-coil processed high-magnetic-induction oriented steel is tested, the three-coil processed high-magnetic-induction oriented steel is marked as coil I, coil II and coil III, the coil I, the coil II and the coil III are medium-sized coils, the total amount of which reaches 7.9 tons, and the data in the table 2 are obtained after the iron loss condition test.
TABLE 2
As can be seen from the data in Table 2, the minimum iron loss reaches 0.99w/kg, compared with the iron loss value of 1.5-2w/kg in the prior art, the process obviously achieves the purpose of reducing the iron loss, simultaneously the first coil, the second coil and the third coil all reach the level of 27QG110, and the performance of the whole high magnetic induction oriented steel is improved.
Example 2
Embodiment 2 is different from embodiment 1 in that the coating apparatus shown in fig. 1, fig. 2 and fig. 3 is used in step 9, and includes a frame (not shown), a conveying mechanism, a coating mechanism and a winding mechanism, the conveying mechanism includes a conveyor belt 10 for horizontally conveying to the left and a rectangular stop frame 101 in a shape of n, an opening on the lower side of the rectangular stop frame 101 contacts with the upper surface of the conveyor belt 10, and the rectangular stop frame 101 is welded to the frame. As shown in fig. 1, when the steel plate 60 is conveyed to the rectangular position-limiting frame 101 by the conveyor belt 10, the upper surface of the conveyor belt 10 is attached to the lower surface of the steel plate 60, the upper inner wall of the rectangular position-limiting frame 101 can be in sliding contact with the upper surface of the steel plate 60, and the vertical inner wall of the rectangular position-limiting frame 101 is in contact with the vertical side surface of the steel plate 60.
As shown in fig. 1 and fig. 2, the coating mechanism includes a container 20 welded on the rack, a flow guide pipe 201 and a rectangular coating block 202, the coating block 202 is vertically arranged, the coating block 202 is provided with a coating hole 203 along a horizontal axial direction, a flow guide cavity 204 is arranged in the coating block 202, the container 20, the flow guide pipe 201 and the flow guide cavity 204 in the coating block 202 are sequentially communicated from top to bottom, the container 20 is welded with the flow guide pipe 201, and the flow guide pipe 201 is welded with the coating block 202; the inner wall of the coating hole 203 is provided with a plurality of communicating holes 205 communicated with the flow guide cavity 204, and the inner wall of the coating hole 203 is covered with sponge 206; the axis in the horizontal direction of the coating hole 203 is collinear with the axis when the steel plate 60 is conveyed.
As shown in fig. 1 and 3, the winding mechanism is arranged on the left side of the coating mechanism, the winding mechanism includes two support columns 30 and two support units, the two support columns 30 are symmetrically arranged along the horizontal axis of the coating hole 203, the support units include a reel 401, support bearings 402, a spring rod 403 and a pressure spring 404 sleeved on the spring rod 403, the upper end of the pressure spring 404 is welded with the upper end of the spring rod 403, the lower end of the pressure spring 404 is welded with the lower end of the spring rod 403, the lower end of the spring rod 403 is welded with the lower end of the support column 30, the axes of the two support bearings 402 are horizontally and coaxially arranged, the side surfaces of the support bearings 402 are welded with the top end of the spring rod 403, the two ends of the reel 401 are respectively coaxially connected with the two support bearings; as shown in fig. 3, a fixing plate 405 is disposed between the top ends of the two supporting columns 30, the upper end of the fixing plate 405 is welded to the upper supporting column 30, the lower end of the fixing plate 405 is welded to the lower supporting column 30, and as shown in fig. 1, the lower surface of the fixing plate 405 is coplanar with the upper surface of the steel plate 60 during the transportation.
Compared with the embodiment 1, the production process of the high magnetic induction oriented steel in the embodiment has the following difference when in use, when the insulating coating film is coated in the step 9, the steel plate 60 after high temperature annealing is moved to the right end of the conveyor belt 10, the conveyor belt 10 conveys the steel plate 60 to the left side, when the steel plate is conveyed to the rectangular limit frame 101, only a single layer of steel plate 60 can pass through due to the limitation of the gap between the rectangular limit frame 101 and the upper surface of the conveyor belt 10, and at the moment, the rectangular limit frame 101 levels and limits the steel plate 60 in the conveying process; when the steel plate 60 moves to the coating mechanism, the coating raw material in the containing box 20 enters the sponge 206 through the containing box 20, the guide pipe 201, the flow guide cavity 204 in the coating block 202 and the communication holes 205 on the inner wall of the coating hole 203 in sequence, when the steel plate 60 passes through the coating hole 203, the sponge 206 is in contact with each surface of the steel plate 60, the sponge 206 is squeezed, and the coating raw material in the sponge 206 is coated on each surface of the steel plate 60 to form a uniform insulating coating film; at this time, the conveyor belt 10 continues to convey the steel plate 60 to the left onto the reel 401, when the steel plate 60 is preliminarily wound on the rotating shaft, two ends of the rotating shaft are respectively fixed in the two supporting bearings 402, and the rotating shaft is positioned at the upper ends of the supporting columns 30 under the support of the supporting bearings 402; when the steel plate 60 is continuously conveyed to the left side, the lower surface of the fixing plate 405 is continuously contacted with the upper surface of the steel plate 60, the steel plates 60 wound on the rotating shaft are sequentially increased, the rotating shaft and the supporting bearing 402 press the supporting rod and the spring to move downwards, and the fixing plate 405 also presses the steel plate 60 to move downwards, so that a space is increased for the subsequent winding of the steel plate 60; when the support rod and the spring move downwards to the limit or the space between the two support columns 30 is not enough for winding the steel plate 60, the rotating shaft buckled on the support bearing 402 is disassembled, so that the coating of the insulating coating film on the steel plate 60 is realized in the process, and the subsequent stretching annealing is convenient; meanwhile, the steel plate 60 coated with the insulating coating film can be wound and collected, and the processing efficiency of the high-magnetic-induction oriented steel can be effectively improved.
Claims (10)
1. The production process of the high magnetic induction oriented steel is characterized by comprising the following steps of:
step 1: preparing steel for steelmaking, and carrying out steelmaking on the steel by adopting a converter or an electric furnace to obtain molten steel; carrying out vacuum degassing treatment on the molten steel to obtain a silicon steel continuous casting slab;
step 2: heating the silicon steel continuous casting slab at the temperature of 1150-1300 ℃ to enable the temperature of the silicon steel continuous casting slab to reach 1150-1300 ℃, then carrying out rough rolling on the silicon steel continuous casting slab to 40-70mm, and then carrying out fine rolling on the silicon steel continuous casting slab, wherein the cumulative reduction rate of the fine rolling is more than 90%;
and step 3: after the finish rolling, rapidly cooling the hot-rolled silicon steel plate, and then coiling the steel plate, wherein the temperature of the coiled steel plate is below 600 ℃;
and 4, step 4: normalizing the steel plate by adopting two-stage normalization;
and 5: performing cold rolling processing on the normalized steel plate, wherein the final reduction rate of the cold rolling is more than 80%, and the temperature of the steel plate is kept at 190-210 ℃ during the cold rolling;
step 6: introducing the cold-rolled steel plate into a continuous annealing furnace for decarburization annealing, adopting a protective atmosphere when the steel plate is heated to 770-900 ℃, and adopting the oxidation degree (P) of the protective atmosphereH2O/PH2)0.35-0.45, and the concentration of carbon element is less than or equal to 25ppm, and the concentration of oxygen element is 600-700 ppm;
and 7: after decarburization annealing, introducing ammonia gas with higher nitriding energy into the independent furnace section of the annealing furnace in the step 6, so that the ratio of the nitrogen element content in the steel plate to the aluminum element content in the steel plate is more than 2: 4;
and 8: coating an annealing release agent on the surface of the steel plate subjected to the nitriding treatment in the step 7;
and step 9: annealing the steel plate at high temperature to generate recrystallized grains with the orientation of {110} <100 >;
step 10: coating an insulating coating film on the surface of the steel plate subjected to high-temperature annealing, and then performing stretching annealing;
step 11: and carrying out laser scoring on the steel plate after the stretching annealing.
2. The process for treating high magnetic induction oriented steel according to claim 1, wherein in the step 2, the reduction ratio of the final pass of the finish rolling is 25% or more.
3. The process for treating high magnetic induction oriented steel according to claim 2, wherein in the step 2, the reduction ratio of the final pass of the finish rolling is 30% or more.
4. The process for treating high magnetic induction oriented steel according to claim 3, wherein in the step 4, when the steel plate is normalized by two-stage normalization, in the first stage of heating normalization, the temperature rise speed is 5-10 ℃/s, when the temperature rises to over 1100 ℃, the temperature is kept for 30 seconds, and then the temperature is immediately reduced; in the second stage of heating and normalizing, the annealing speed is more than or equal to 6 ℃/s, the crystal grain structure in the steel plate keeps the lamellar interval, and the cooling speed is 50 ℃/s.
5. The process of claim 4, wherein the grain structure in the steel plate is maintained at lamellar intervals, and the lamellar intervals reach 20 μm.
6. The process of claim 5, wherein in the step 7, after the nitriding treatment, the ratio of the content of nitrogen element in the steel plate to the content of aluminum element in the steel plate is greater than 2: 3.
7. The process of claim 6, wherein the thickness of the insulating coating film in step 10 is 4.0-5.0g/m2。
8. The process of claim 7, wherein the thickness of the insulating coating film in step 10 is 4.5g/m2。
9. The process as claimed in claim 8, wherein the temperature of the steel sheet in the cold rolling process is maintained at 195-205 ℃.
10. The process for treating high magnetic induction oriented steel according to claim 9, wherein in the step 6, the annealing separator is MgO annealing separator or TiO2 annealing separator.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN113319524A (en) * | 2021-04-16 | 2021-08-31 | 包头市威丰稀土电磁材料股份有限公司 | Manufacturing method for reducing iron loss of oriented silicon steel by laser scoring |
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| KR900004851B1 (en) * | 1986-12-31 | 1990-07-08 | 포항종합제철 주식회사 | Making process for oriented silicon plate |
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| CN108546814A (en) * | 2018-04-11 | 2018-09-18 | 北京科技大学 | A method of high magnetic induction grain-oriented silicon steel is produced based on ESP Endless Rolling Technologies |
| CN209023871U (en) * | 2018-09-26 | 2019-06-25 | 浙江华赢特钢科技有限公司 | A kind of silicon steel winding device of handling up automatically |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN113319524A (en) * | 2021-04-16 | 2021-08-31 | 包头市威丰稀土电磁材料股份有限公司 | Manufacturing method for reducing iron loss of oriented silicon steel by laser scoring |
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