CN116004961A - Preparation method of oriented silicon steel and oriented silicon steel - Google Patents
Preparation method of oriented silicon steel and oriented silicon steel Download PDFInfo
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- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 67
- 238000002360 preparation method Methods 0.000 title claims abstract description 13
- 238000000137 annealing Methods 0.000 claims abstract description 111
- 238000005121 nitriding Methods 0.000 claims abstract description 89
- 238000005266 casting Methods 0.000 claims abstract description 85
- 238000005261 decarburization Methods 0.000 claims abstract description 81
- 238000009749 continuous casting Methods 0.000 claims abstract description 78
- 238000000034 method Methods 0.000 claims abstract description 70
- 238000005098 hot rolling Methods 0.000 claims abstract description 48
- 239000011248 coating agent Substances 0.000 claims abstract description 46
- 238000000576 coating method Methods 0.000 claims abstract description 46
- 238000005097 cold rolling Methods 0.000 claims abstract description 28
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 26
- 239000010959 steel Substances 0.000 claims abstract description 26
- 238000004519 manufacturing process Methods 0.000 claims abstract description 19
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 10
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims description 31
- 230000006698 induction Effects 0.000 claims description 25
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 20
- 238000005096 rolling process Methods 0.000 claims description 19
- 230000000630 rising effect Effects 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 239000010960 cold rolled steel Substances 0.000 claims description 3
- 239000003112 inhibitor Substances 0.000 abstract description 39
- 239000000126 substance Substances 0.000 abstract description 39
- 239000002131 composite material Substances 0.000 abstract description 4
- 239000013078 crystal Substances 0.000 description 40
- 230000000052 comparative effect Effects 0.000 description 39
- 239000000203 mixture Substances 0.000 description 34
- 238000001953 recrystallisation Methods 0.000 description 20
- 239000000047 product Substances 0.000 description 18
- 238000010606 normalization Methods 0.000 description 7
- 239000002244 precipitate Substances 0.000 description 7
- 239000000395 magnesium oxide Substances 0.000 description 5
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 5
- 238000001035 drying Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 230000005764 inhibitory process Effects 0.000 description 4
- 206010010356 Congenital anomaly Diseases 0.000 description 3
- 238000005554 pickling Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000003966 growth inhibitor Substances 0.000 description 1
- HCWCAKKEBCNQJP-UHFFFAOYSA-N magnesium orthosilicate Chemical compound [Mg+2].[Mg+2].[O-][Si]([O-])([O-])[O-] HCWCAKKEBCNQJP-UHFFFAOYSA-N 0.000 description 1
- 239000000391 magnesium silicate Substances 0.000 description 1
- 229910052919 magnesium silicate Inorganic materials 0.000 description 1
- 235000019792 magnesium silicate Nutrition 0.000 description 1
- AXZKOIWUVFPNLO-UHFFFAOYSA-N magnesium;oxygen(2-) Chemical compound [O-2].[Mg+2] AXZKOIWUVFPNLO-UHFFFAOYSA-N 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 235000012239 silicon dioxide Nutrition 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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Abstract
The application provides a preparation method of oriented silicon steel and the oriented silicon steel. The preparation method of the oriented silicon steel provided by the application comprises the following steps: carrying out continuous casting treatment on the molten steel to obtain a casting blank; the casting blank comprises the following components in percentage by mass: c:0.03-0.09%, si:2.8-4.4%; als:0.015-0.030%, N:0.0050-0.0095%, mn:0.1-0.4%, sb:0.01-0.05%, cu 0.05-0.25%, S:0.01-0.03%, ni:0.05-0.2%, and the balance of Fe and unavoidable impurities; and carrying out hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating and stretching flattening annealing treatment on the casting blank to obtain the oriented silicon steel. According to the method, the chemical components of the steel are optimized, a composite inhibitor system is adopted, different main inhibitors are adopted in different annealing stages, so that the normalizing is omitted, meanwhile, good magnetic performance is ensured, the process is simplified, the equipment investment is reduced, and the production cost is reduced.
Description
Technical Field
The application relates to the technical field of steel preparation, in particular to a preparation method of oriented silicon steel and the oriented silicon steel.
Background
Oriented silicon steel is an important soft magnetic functional material and is mainly used as various transformer cores. It is characterized by excellent magnetic properties in the rolling direction, which are obtained by secondary recrystallization: that is, the growth of normal grains is inhibited by the grain growth inhibitor, so that grains with certain special orientations engulf the normal grains and abnormal growth occurs.
The production method of the oriented silicon steel can be classified into an congenital type and a acquired type according to the obtaining mode of the inhibitor. Because the inherent inhibitor oriented silicon steel needs to fully dissolve coarse precipitate particles precipitated in a casting blank, a high hot rolling heating temperature is needed, and the problems of high energy consumption, low efficiency and frequent maintenance of a heating furnace are caused. The inhibitor can be supplemented by the poststep, so that the low hot rolling heating temperature can be adopted, the production cost is greatly reduced, and the method becomes the main production method of the current oriented silicon steel.
However, the prior art of acquired suppression type high magnetic induction oriented silicon steel basically needs to be standardized. Normalization brings three problems: 1) The equipment investment is increased; 2) The process flow is complex; 3) The production cost increases.
Disclosure of Invention
The embodiment of the application provides a preparation method of oriented silicon steel and the oriented silicon steel, and aims to prepare the oriented silicon steel by a normalizing-free method so as to reduce cost, enhance efficiency, save energy and reduce emission.
In a first aspect, an embodiment of the present application provides a method for preparing oriented silicon steel, including: carrying out continuous casting treatment on the molten steel to obtain a casting blank; the casting blank comprises the following components in percentage by mass: c:0.03-0.09%, si:2.8-4.4%; als:0.015-0.030%, N:0.0050-0.0095%, mn:0.1-0.4%, sb:0.01-0.05%, cu 0.05-0.25%, S:0.01-0.03%, ni:0.05-0.2%, and the balance of Fe and unavoidable impurities; and carrying out hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating and stretching flattening annealing treatment on the casting blank to obtain the oriented silicon steel.
According to an embodiment of the first aspect of the present application, in the step of obtaining the cast slab, the equiaxed crystal rate in the cast slab is 20% to 60%.
According to an embodiment of the first aspect of the present application, the hot rolling process comprises: and heating the continuous casting blank to 1150-1280 ℃ for hot rolling, and controlling the hot rolling finishing temperature to 890-970 ℃ to obtain the hot rolled steel plate.
According to an embodiment of the first aspect of the present application, the cold rolling process comprises: and (3) performing primary cold rolling or secondary cold rolling with intermediate annealing on the hot-rolled steel plate to obtain the cold-rolled steel plate, wherein the reduction rate of the cold rolling treatment is more than or equal to 70%.
According to an embodiment of the first aspect of the present application, the decarburization temperature satisfies 790 to 900 ℃ at the time of the decarburization nitriding annealing treatment.
According to an embodiment of the first aspect of the present application, the temperature increase rate v in the temperature range of 500 ℃ to 750 ℃ satisfies 40 ℃ to 70 ℃/s when the decarburization nitriding annealing treatment is performed.
According to an embodiment of the first aspect of the present application, the decarburization nitriding annealing treatment includes: at H 2 +N 2 +NH 3 And (3) carrying out continuous decarburization nitriding annealing on the steel strip in the atmosphere, wherein the nitriding temperature is 800-950 ℃, and the nitriding amount b is 150-300 ppm.
According to an embodiment of the first aspect of the present application, the step of obtaining oriented silicon steel further includes: after decarburization nitriding annealing treatment, mgO is coated on the surface of the steel, and high-temperature annealing treatment is performed after drying.
In a second aspect, the present application provides an oriented silicon steel, which is prepared by the foregoing method, and includes the following components in percentage by mass: c:0.03-0.09%, si:2.8-4.4%; als:0.015-0.030%, N:0.0050-0.0095%, mn:0.1-0.4%, sb:0.01-0.05%, cu 0.05-0.25%, S:0.01-0.03%, ni:0.05-0.2%, and the balance of Fe and unavoidable impurities.
According to an embodiment of the second aspect of the present application, magnetic induction B 8 The value range of (2) satisfies B 8 More than or equal to 1.89T, iron loss P 17/50 The value range of (2) satisfies P 17/50 ≤1.05W/kg。
Compared with the prior art, the invention has at least the following beneficial effects:
the application provides a preparation method of oriented silicon steel, which adopts a composite inhibitor system by optimizing chemical components of steel and adopts different main inhibitors in different annealing stages, thereby omitting normalization and ensuring good magnetic performance. Simplifying the process, reducing the equipment investment and lowering the production cost.
Specifically, al and N are added to the composition as inhibitor forming elements to form AlN precipitates, which play a role in mainly inhibiting the normal growth of primary grains before the start of secondary recrystallization, the Als content is less than 0.015% or the N content is less than 0.005%, and the amount of the effective inhibitor formed is eventually insufficient, and the inhibitor strength required for completing secondary recrystallization is not obtained; the content of Als is higher than 0.030% or the content of N is lower than 0.0095%, and the solubility product of Als and N is too large, so that coarse AlN in a casting blank is difficult to be completely dissolved in a solid state during hot rolling heating, and the amount of AlN serving as an effective inhibitor is insufficient finally.
Sb is added into the components to serve as grain boundary segregation elements and serve as auxiliary inhibitors, the content of Sb is lower than 0.01% and cannot reach the effect of the auxiliary inhibitors, and the content of Sb exceeds 0.05% can cause serious deterioration of surface quality.
Cu and S are added into the components to form CuxS, the CuxS is used as a main inhibitor in the primary recrystallization process, the Cu is lower than 0.05 percent or the S is lower than 0.01 percent, the amount of the inhibitor is too small, the Cu is higher than 0.26 percent or the S is higher than 0.03 percent, the required hot rolling heating temperature is too high, and the production difficulty is large.
The addition of suitable Ni to the composition is mainly to improve the uniformity of the primary recrystallized structure.
Detailed Description
Embodiments of the present application are described in further detail below in conjunction with examples. The following detailed description of the embodiments is provided to illustrate the principles of the present application and is not intended to limit the scope of the application, i.e., the application is not limited to the embodiments described.
In the description of the present application, it is to be noted that, unless otherwise indicated, the meaning of "plurality" is two or more; the terms "upper," "lower," "left," "right," "inner," "outer," and the like indicate an orientation or positional relationship merely for convenience of description and to simplify the description, and do not indicate or imply that the devices or elements being referred to must have a particular orientation, be constructed and operated in a particular orientation, and thus are not to be construed as limiting the present application. Furthermore, the terms "first," "second," and the like are used for descriptive purposes only and are not to be construed as indicating or implying relative importance. The term "vertical" does not require a strict sense of vertical, but may include an allowable error. "parallel" does not require parallelism in a strict sense, but may include an allowable error.
The traditional production process route of the acquired inhibitor oriented silicon steel comprises steelmaking, hot rolling, normalized pickling, cold rolling, decarburization nitriding, magnesium oxide coating, high-temperature annealing, coating and stretching leveling annealing. Annealing, i.e., normalizing, of hot rolled sheet is a critical process in the production of high magnetic induction oriented silicon steel, and the normalizing effect is different for congenital and acquired oriented silicon steels. For the congenital oriented silicon steel, normalization is the final and most critical process for determining the form and quantity of inhibitor; for the acquired version, the effect of normalization is to improve the tissue and form part of the inhibitor, the final definition of which is to be at decarbonizing and high temperature annealing.
The prior art of the high magnetic induction oriented silicon steel of the acquired inhibitor basically needs to be standardized, which increases equipment investment and production cost, and the high temperature coiling is used for replacing the standardized high magnetic induction oriented silicon steel, so that the performance of a finished product is unstable due to insufficient inhibition capability.
In view of this, the embodiment of the application provides a preparation method of oriented silicon steel and oriented silicon steel, and the preparation method provided by the embodiment of the application adopts a composite inhibitor system, adopts different main inhibitors in different annealing stages, and ensures good magnetic performance while omitting normalization, simplifies the process, and can reduce equipment investment and production cost.
Preparation method of oriented silicon steel
In a first aspect, an embodiment of the present application provides a method for preparing oriented silicon steel, including: carrying out continuous casting treatment on the molten steel to obtain a casting blank; the casting blank comprises the following components in percentage by mass: c:0.03-0.09%, si:2.8-4.4%; als:0.015-0.030%, N:0.0050-0.0095%, mn:0.1-0.4%, sb:0.01-0.05%, cu 0.05-0.25%, S:0.01-0.03%, ni:0.05-0.2%, and the balance of Fe and unavoidable impurities; and carrying out hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating and stretching flattening annealing treatment on the casting blank to obtain the oriented silicon steel.
Oriented silicon steel obtains good magnetic properties by secondary recrystallization, which occurs depending on two conditions: 1) Primary recrystallized grain size; 2) Size and distribution of inhibitors. The primary recrystallization is completed in the decarburization annealing process, and a certain size and quantity of primary recrystallization inhibitor are needed before the decarburization annealing in order to obtain a proper primary recrystallization grain size, so that the conventional high-magnetic induction oriented silicon steel with a later-day inhibitor type takes AlN as the primary recrystallization inhibitor, and the AlN is required to be subjected to normalization treatment before the primary cold rolling for fine dispersion precipitation, and further to nitriding treatment after the decarburization annealing in order to obtain a stronger inhibition capability before the secondary recrystallization. In the embodiment of the application, cu is used in the decarburization annealing process by optimizing the chemical composition of the steel x S+ grain boundary segregation element is used as a main inhibitor to control the size of primary recrystallized grains, then (SiAl) N obtained through nitriding is used as a main inhibitor to prevent normal growth of common grains in the high-temperature annealing process, so that Gaussian grains are abnormally grown, secondary recrystallization is completed, a normalizing process can be omitted, and the high-magnetic induction oriented silicon steel is obtained.
Specifically, cu and S are added into the components to form CuxS, the CuxS is used as a main inhibitor in the primary recrystallization process, the Cu is lower than 0.05 percent or the S is lower than 0.01 percent, the amount of the inhibitor is too small, the Cu is higher than 0.26 percent or the S is higher than 0.03 percent, the required hot rolling heating temperature is too high, and the production difficulty is high.
The addition of suitable Ni to the composition is mainly to improve the uniformity of the primary recrystallized structure.
Sb is added into the components to serve as grain boundary segregation elements and serve as auxiliary inhibitors, the content of Sb is lower than 0.01% and cannot reach the effect of the auxiliary inhibitors, and the content of Sb exceeds 0.05% can cause serious deterioration of surface quality.
Al and N are added into the components as inhibitor forming elements to form AlN precipitates, the AlN precipitates play a role in mainly inhibiting the normal growth of primary grains before secondary recrystallization starts, the Als content is lower than 0.015 percent or the N content is lower than 0.005 percent, and the quantity of the effective inhibitor is finally formed, so that the strength of the inhibitor required for completing secondary recrystallization is not obtained; the content of Als is higher than 0.030% or the content of N is higher than 0.0095%, and the solubility product of Als and N is too large, so that coarse AlN in a casting blank is difficult to be completely dissolved in a solid state during hot rolling heating, and the amount of AlN serving as an effective inhibitor is insufficient finally.
After the insulating layer is coated, the steel strip surface can be subjected to stretching leveling annealing to form a sintered insulating coating, so that insulating performance is provided for the oriented silicon steel, and eddy current loss of the oriented silicon steel in the later use process is reduced.
In some embodiments, the method further comprises a treatment step of laser scoring after the stretching and leveling annealing treatment, wherein the laser scoring can further reduce the iron loss of the oriented silicon steel and improve the quality of the oriented silicon steel.
According to the preparation method of the oriented silicon steel, the chemical components of steel are optimized, a composite inhibitor system is adopted, different main inhibitors are adopted in different annealing stages, normalization is omitted, good magnetic performance is guaranteed, the process is simplified, equipment investment can be reduced, and production cost is reduced.
In some embodiments, in the step of obtaining the cast slab, the medium-axis crystal ratio of the cast slab has a value ranging from 20% to 60%.
The cooling intensity and the electromagnetic stirring parameters are controlled in the continuous casting process, the equiaxial crystal rate of the casting blank is controlled below 60% by controlling the continuous casting process, a large number of coarse precipitates are prevented from being formed, and a foundation is laid for full solid solution of the precipitates during hot rolling heating.
In some embodiments, the hot rolling process comprises: and heating the continuous casting billet to 1150-1280 ℃ for hot rolling, and controlling the final rolling temperature of the hot rolling to 890-970 ℃ to obtain a hot rolled steel plate.
The casting blank needs to control the solid solution and precipitation of the temperature control inhibitor in the heating and rolling processes in the hot rolling process. When the heating temperature is lower than 1150 ℃, coarse precipitates in a casting blank are difficult to be fully dissolved, and when the heating temperature is higher than 1280 ℃, slag accumulation in a heating furnace is serious, the quality of the edge part of a plate blank is deteriorated, the energy consumption is increased, and the burning loss is increased. When the final rolling temperature is lower than 890 ℃, a large amount of coarse AlN and Cu are precipitated before finishing rolling x S, the effective inhibition dose is seriously insufficient, and the hot rolling finishing temperature is higher thanThe temperature of 970 ℃ is unfavorable for fine dispersion precipitation of CuxS, and the rolling fault rate is easy to increase. The hot rolling is performed in the above temperature range, and a final product satisfying excellent performance quality requirements can be obtained.
In some embodiments, in the step of obtaining a cold-rolled steel sheet, the reduction a of cold rolling satisfies a.gtoreq.70%.
According to embodiments of the present application, when the cold rolling reduction is higher than 70%, for example, the reduction is 75%, 78%, 80%, 82%, and 85%. According to the embodiment of the application, the rolling reduction is set to 75% -85%, so that the accurate Gaussian orientation is obtained, the Gaussian texture is the root cause of excellent magnetic performance of the silicon steel, and meanwhile, the uniformity of crystal grains is improved, and the iron loss of a steel product is reduced.
In some embodiments, the decarburization temperature satisfies 790 to 900 ℃ when the decarburization nitriding annealing treatment is performed.
The decarburization temperature lower than 790 ℃ can lead to the reduction of the C diffusion rate, the decarburization is difficult, the decarburization temperature higher than 900 ℃ is difficult, primary grains grow and coarsen, and secondary recrystallization failure is easy to cause.
In some embodiments, the temperature increase rate v in the temperature range of 500-750 ℃ is in the range of 40-70 ℃/s when the continuous decarburization nitriding annealing is performed.
The decarburization nitriding annealing adopts rapid heating, the rapid heating is performed below the Curie temperature, the heating temperature is controlled to be higher than 40 ℃/s, the excessive release of cold-rolled stored energy before the recrystallization starts is prevented, and the large nucleation rate is realized in the recrystallization process, so that a fine and uniform primary recrystallization structure is obtained.
In some embodiments, the decarburization nitriding treatment comprises: at H 2 +N 2 +NH 3 And (3) carrying out continuous nitriding annealing on the steel strip in the atmosphere, wherein the nitriding temperature is 800-950 ℃, and the nitriding amount b is 150-300 ppm.
After nitriding treatment, a secondary recrystallization inhibitor is easy to form, the nitriding efficiency is too low when the nitriding temperature is lower than 800 ℃, and primary grain growth coarsening is caused when the nitriding temperature is higher than 950 ℃. The nitriding amount is controlled to be in the range of 150-300ppm, the inhibition capability is insufficient below 150ppm, the secondary recrystallization is unstable above 300ppm, and the defects of the bottom layer are increased.
In some embodiments, after nitriding annealing treatment, the method further comprises the steps of coating MgO on the surface of silicon steel, drying and then carrying out high-temperature annealing treatment.
The MgO coating can play a role of a separating agent to prevent the strip steel from adhering in a high-temperature annealing stage, can remove impurities such as nitrogen, sulfur and the like in the steel, and reacts with silicon dioxide on the surface of silicon steel to form an excellent magnesium silicate insulating bottom layer.
In a second aspect, the present application provides an oriented silicon steel, which is prepared by the foregoing method, and includes the following components in percentage by mass: c:0.03-0.09%, si:2.8-4.4%; als:0.015-0.030%, N:0.0050-0.0095%, mn:0.1-0.4%, sb:0.01-0.05%, cu 0.05-0.25%, S:0.01-0.03%, ni:0.05-0.2%, and the balance of Fe and unavoidable impurities.
The oriented silicon steel provided by the embodiment of the application has good magnetic performance and can be used for producing transformer cores.
In some embodiments, magnetic induction B 8 The value range of (2) satisfies B 8 More than or equal to 1.89T, iron loss P 17/50 The value range of (2) satisfies P 17/50 ≤1.05W/kg。
Examples
The following examples more particularly describe the disclosure of the present application, which are intended as illustrative only, since numerous modifications and variations within the scope of the disclosure will be apparent to those skilled in the art. Unless otherwise indicated, all parts, percentages, and ratios reported in the examples below are by weight, and all reagents used in the examples are commercially available or were obtained synthetically according to conventional methods and can be used directly without further treatment, as well as the instruments used in the examples.
Example 1 a cast slab was obtained by continuous casting of the chemical composition described in example 1 of table 1, and the equiaxed crystal ratio of the cast slab structure obtained by adjusting the continuous casting process parameters was 35% -45%. The casting blank is heated in a heating furnace at 1260 ℃ for 100min, then hot rolled to a thickness of 2.3mm, the hot rolling start temperature is 1142 ℃, and the final rolling temperature is 938 ℃. The hot rolled plate is cold rolled to a thickness of 0.27mm after pickling. The cold rolled coil is subjected to decarburization annealing, wherein the temperature rising rate of the temperature section of 500-750 ℃ is 60 ℃/s, the decarburization annealing temperature is 833 ℃, the nitriding annealing is performed after the decarburization annealing, the nitriding temperature is 880 ℃, and the nitriding amount is 200ppm. And (3) coating MgO after nitriding, drying, carrying out high-temperature annealing according to the traditional process, coating an insulating layer after high-temperature annealing, stretching and leveling annealing, and carrying out laser scoring after stretching and leveling annealing.
Example 2
Casting blanks are obtained by continuous casting according to the chemical components in the embodiment 2 of the table 1, and the equiaxed crystal rate of the casting blank tissue obtained by adjusting the continuous casting process parameters is 35% -45%. The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Example 3
Casting blanks are obtained by continuous casting according to the chemical components in the embodiment 3 of the table 1, and the equiaxed crystal rate of the casting blank tissue obtained by adjusting the continuous casting process parameters is 35% -45%. The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Example 4
Casting blanks are obtained by continuous casting according to the chemical components in the embodiment 4 of the table 1, and the equiaxed crystal rate of the casting blank tissue obtained by adjusting the continuous casting process parameters is 35% -45%. The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Example 5
Casting blanks are obtained by continuous casting according to the chemical components in the embodiment 5 of the table 1, and the equiaxed crystal rate of the casting blank tissue obtained by adjusting the continuous casting process parameters is 35% -45%. The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Example 6
Casting billets were obtained according to the chemical composition continuous casting of example 1 in table 1, and the equiaxed crystal ratio of the casting billet structure obtained by adjusting the continuous casting process parameters was 21%. The casting blank is heated in a heating furnace at 1250 ℃ for 90min and then hot rolled to a thickness of 2.22mm, the hot rolling start temperature is 1130-1140 ℃, and the final rolling temperature is 930-1000 ℃. The hot rolled plate is cold rolled to a thickness of 0.27mm after pickling. The cold rolled coil is subjected to decarburization annealing, wherein the temperature rise rate of the temperature section of 500-750 ℃ is 55 ℃/s, the decarburization annealing temperature is 840 ℃, the nitriding annealing is performed after the decarburization annealing, the nitriding temperature is 860 ℃, and the nitriding amount is 210ppm. And (3) coating MgO after nitriding, drying, carrying out high-temperature annealing according to the traditional process, coating an insulating layer after high-temperature annealing, stretching and leveling annealing, and carrying out laser scoring after stretching and leveling annealing.
Example 7
Casting billets were obtained according to the chemical composition continuous casting of example 1 in table 1, and the equiaxed crystal ratio of the casting billet structure obtained by adjusting the continuous casting process parameters was 33%. The subsequent treatment was the same as that of example 6, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Example 8
Casting billets were obtained according to the chemical composition continuous casting of example 1 in table 1, and the equiaxed crystal ratio of the casting billet structure obtained by adjusting the continuous casting process parameters was 46%. The subsequent treatment was the same as that of example 6, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Example 9
Casting billets were obtained according to the chemical composition continuous casting of example 1 in table 1, and the equiaxed crystal ratio of the casting billet structure obtained by adjusting the continuous casting process parameters was 54%. The subsequent treatment was the same as that of example 6, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Example 10
Casting billets were obtained according to the chemical composition continuous casting of example 1 in table 1, and the equiaxed crystal ratio of the casting billet structure obtained by adjusting the continuous casting process parameters was 56%. The subsequent treatment was the same as that of example 6, hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching and leveling annealing.
Example 11
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment of example 11 in table 3 were conducted at the time of hot rolling.
Example 12
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment of example 12 in table 3 were conducted at the time of hot rolling.
Example 13
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment of example 13 in table 3 were conducted at the time of hot rolling.
Example 14
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment according to example 14 in table 3 were conducted at the time of hot rolling.
Example 15
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring of example 5, except that the continuous annealing was performed at a temperature section of 500 to 750 ℃ in the temperature section of example 15 in table 4, at a temperature rise rate, at a decarburization temperature, at a nitriding temperature, and at a nitriding amount.
Example 16
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature section of 500 to 750 ℃ in the temperature section of example 16 in table 4 at a temperature rising rate, decarburization temperature, nitriding amount.
Example 17
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature section of 500 to 750 ℃ in the temperature section of example 17 in table 4 at a temperature rising rate, decarburization temperature, nitriding amount.
Example 18
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature section of 500 to 750 ℃ in the temperature section of example 18 in table 4 at a temperature rising rate, decarburization temperature, nitriding amount.
Example 19
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature section of 500 to 750 ℃ in the temperature section of example 19 in table 4 at a temperature rising rate, decarburization temperature, nitriding amount.
Comparative example 1
Casting blanks are obtained through continuous casting according to the chemical components in the comparative example 1 of the table 1, and the equiaxial crystal rate of the casting blank tissue obtained through adjusting the continuous casting process parameters is 35% -45%. The subsequent treatment was the same as that of comparative example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Comparative example 2
Casting blanks are obtained through continuous casting according to the chemical components in the comparative example 2 of the table 1, and the equiaxial crystal rate of the casting blank tissue obtained through adjusting the continuous casting process parameters is 35% -45%. The subsequent treatment was the same as that of comparative example 2, hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating, stretching and leveling annealing-laser scoring.
Comparative example 3
Casting blanks are obtained through continuous casting according to the chemical components in the comparative example 3 of the table 1, and the equiaxial crystal rate of the casting blank tissue obtained through adjusting the continuous casting process parameters is 35% -45%. The subsequent treatment was the same as that of comparative example 3, hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating, stretching and leveling annealing-laser scoring.
Comparative example 4
Casting billets were obtained by continuous casting according to the chemical composition described in example 1 of table 1, and the equiaxed crystal ratio of the cast billet structure obtained by adjusting the continuous casting process parameters was (63%). The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Comparative example 5
Casting billets were obtained by continuous casting according to the chemical composition described in example 1 of table 1, and the equiaxed crystal ratio of the cast billet structure obtained by adjusting the continuous casting process parameters was (67%). The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Comparative example 6
Casting billets were obtained by continuous casting according to the chemical composition described in example 1 of table 1, and the equiaxed crystal ratio of the cast billet structure obtained by adjusting the continuous casting process parameters was (72%). The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Comparative example 7
Casting billets were obtained by continuous casting according to the chemical composition described in example 1 of table 1, and the equiaxed crystal ratio of the cast billet structure obtained by adjusting the continuous casting process parameters was (77%). The subsequent treatment was the same as that of example 1, hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating, stretching and leveling annealing, and laser scoring.
Comparative example 8
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment according to comparative example 8 in table 3 were conducted at the time of hot rolling.
Comparative example 9
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment according to comparative example 9 in table 3 were conducted at the time of hot rolling.
Comparative example 10
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment according to comparative example 10 in table 3 were conducted at the time of hot rolling.
Comparative example 11
Casting blanks were obtained according to the chemical composition continuous casting of example 4 in table 1, and the equiaxed crystal ratio of the casting blank tissue obtained by adjusting the continuous casting process parameters was 45% -55%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 4, except that the slab heating temperature and finish rolling finishing temperature treatment according to comparative example 11 in table 3 were conducted at the time of hot rolling.
Comparative example 12
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature-raising rate, decarburization temperature, nitriding amount in the temperature section of 500 to 750 ℃ of comparative example 12 in table 4.
Comparative example 13
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature-raising rate, decarburization temperature, nitriding amount in the temperature section of 500 to 750 ℃ of comparative example 13 in table 4.
Comparative example 14
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature section of 500 to 750 ℃ in comparative example 14 in table 4 at a temperature rising rate, decarburization temperature, nitriding amount.
Comparative example 15
Casting blanks were obtained according to the chemical composition continuous casting of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature section of 500 to 750 ℃ in comparative example 15 in table 4 at a temperature rising rate, decarburization temperature, nitriding amount.
Comparative example 16
Casting blanks were obtained by continuous casting according to the chemical composition of example 5 in table 1, and the equiaxed crystal ratio of the casting blank structure obtained by adjusting the continuous casting process parameters was 37% -47%. The subsequent treatment was similar to the hot rolling-cold rolling-decarburization nitriding annealing-high temperature annealing-insulating layer coating and stretching flattening annealing-laser scoring treatment of example 5, except that the continuous annealing was conducted at a temperature section of 500 to 750 ℃ in comparative example 16 in table 4 at a temperature rising rate, decarburization temperature, nitriding amount.
The finished product was tested for magnetic properties by the epstein method, and the magnetic properties are shown in tables 1-4.
TABLE 1 magnetic Properties of finished products corresponding to different compositions
TABLE 2 magnetic properties of finished products of different equiaxed grain ratios
TABLE 3 magnetic Properties of finished products corresponding to different Hot Rolling technologies
| Slab heating temperature (DEG C) | Finish rolling finishing temperature (. Degree. C.) | P 17/50 (W/kg) | B 8 (T) | |
| Example 11 | 1153 | 935 | 1.059 | 1.892 |
| Example 12 | 1220 | 945 | 1.008 | 1.902 |
| Example 13 | 1250 | 950 | 0.983 | 1.911 |
| Example 14 | 1280 | 958 | 0.962 | 1.916 |
| Comparative example 8 | 1120 | 875 | 1.358 | 1.812 |
| Comparative example 9 | 1145 | 930 | 1.118 | 1.874 |
| Comparative example 10 | 1276 | 972 | 1.142 | 1.884 |
| Comparative example 11 | 1315 | 975 | 1.137 | 1.879 |
TABLE 4 magnetic Properties of finished products corresponding to different decarburization nitriding Processes
As can be seen from Table 1, the finished product magnetic induction B was obtained in the case where the compositions of the oriented silicon steels of examples 1 to 5 were within the scope of the present application 8 The performance level of the high magnetic induction oriented silicon steel is achieved at more than 1.89T; the steel products of comparative examples 1 to 3 have magnetic induction B in the case where one or more of the steel products is out of the scope of the present invention 8 Below 1.89T, the performance level of the high magnetic induction oriented silicon steel is not achieved.
As can be seen from Table 2, when the equiaxial crystal rate of the cast blank structure of examples 6-10 is above 60%, the average magnetic induction of the corresponding finished products is below 1.89T, and the performance level of the high magnetic induction oriented silicon steel is not achieved; comparative examples 4-7 when the equiaxed grain ratio of the cast blank structure is below 60%, the average magnetic induction of the corresponding finished products is above 1.89T, and the iron loss is below 1.05W/kg, so that the performance level of the high-magnetic induction oriented silicon steel is achieved.
As can be seen from Table 3, when the slab heating temperatures and the hot rolling finishing temperatures of examples 11 to 14 are both within the ranges of the present application, the average magnetic induction of the corresponding finished products is 1.89T or less, and the performance level of the high magnetic induction oriented silicon steel is achieved; when one of the slab heating temperature and the hot rolling finishing temperature of comparative examples 8-11 is not within the scope of the invention, the average magnetic induction of the corresponding finished products is below 1.89T, the iron loss is above 1.10W/kg, and the performance level of the high magnetic induction oriented silicon steel is not achieved.
As can be seen from Table 4, in the cases where the decarburization and nitriding processes of examples 15 to 19 are both within the scope of the present application, the magnetic induction B8 of the finished product is above 1.89T, and the performance level of the high magnetic induction oriented silicon steel is achieved; comparative examples 12-16 finished product magnetic induction B in the case where one or more of decarburization and nitriding processes are out of the scope of the present invention 8 The performance level of the high magnetic induction oriented silicon steel can not be reached under 1.89T.
While the invention has been described with reference to certain preferred embodiments, it will be understood by those skilled in the art that various changes and substitutions of equivalents may be made and equivalents will be apparent to those skilled in the art without departing from the scope of the invention. Therefore, the protection scope of the present application shall be subject to the protection scope of the claims.
Claims (10)
1. The preparation method of the oriented silicon steel is characterized by comprising the following steps:
continuously casting to obtain a casting blank, wherein the casting blank comprises the following components in percentage by mass: c:0.03-0.09%, si:2.8-4.4%; als:0.015-0.030%, N:0.0050-0.0095%, mn:0.1-0.4%, sb:0.01-0.05%, cu 0.05-0.25%, S:0.01-0.03%, ni:0.05-0.2%, and the balance of Fe and unavoidable impurities;
and carrying out hot rolling, cold rolling, decarburization nitriding annealing, high-temperature annealing, insulating layer coating and stretching flattening annealing treatment on the casting blank to obtain the oriented silicon steel.
2. The method for producing oriented silicon steel according to claim 1, wherein in the step of obtaining the cast slab, the equiaxed grain ratio in the cast slab is 20% to 60%.
3. The method for producing oriented silicon steel according to claim 1, wherein the hot rolling treatment comprises: and heating the continuous casting billet to 1150-1280 ℃ for hot rolling, and controlling the final rolling temperature of the hot rolling to 890-970 ℃ to obtain a hot rolled steel plate.
4. The method for producing oriented silicon steel according to claim 3, wherein the cold rolling process comprises: and (3) performing primary cold rolling or secondary cold rolling with intermediate annealing on the hot-rolled steel plate to obtain a cold-rolled steel plate, wherein the reduction rate of the cold rolling treatment is more than or equal to 70%.
5. The method for producing oriented silicon steel according to claim 1, wherein the decarburization temperature satisfies 790 ℃ to 900 ℃ at the time of the decarburization nitriding annealing treatment.
6. The method for producing oriented silicon steel according to claim 5, wherein the temperature rising rate v at a temperature range of 500 ℃ to 750 ℃ satisfies 40 ℃/s to 70 ℃/s when the decarburization nitriding annealing treatment is performed.
7. The method for producing oriented silicon steel according to claim 1, wherein the decarburization nitriding annealing treatment comprises: at H 2 +N 2 +NH 3 And (3) carrying out continuous decarburization nitriding annealing on the steel strip in the atmosphere, wherein the nitriding temperature is 800-950 ℃, and the nitriding amount b is 150-300 ppm.
8. The method of producing oriented silicon steel as claimed in claim 3, wherein the step of obtaining oriented silicon steel further comprises: after the decarburization nitriding annealing treatment, mgO is coated on the surface of the steel, and the high-temperature annealing treatment is performed after the MgO is dried.
9. The oriented silicon steel is characterized by comprising the following components in percentage by mass: c:0.03-0.09%, si:2.8-4.4%; als:0.015-0.030%, N:0.0050-0.0095%, mn:0.1-0.4%, sb:0.01-0.05%, cu 0.05-0.25%, S:0.01-0.03%, ni:0.05-0.2%, and the balance of Fe and unavoidable impurities.
10. The oriented silicon steel according to claim 9, characterized in that the magnetic induction B of the oriented silicon steel 8 The value range of (2) satisfies B 8 More than or equal to 1.89T, iron loss P 17/50 The value range of (2) satisfies P 17/50 ≤1.05W/kg。
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| US20120000262A1 (en) * | 2008-12-31 | 2012-01-05 | Baoshan Iron & Steel Co., Ltd. | Method for manufacturing grain-oriented silicon steel with single cold rolling |
| WO2014032216A1 (en) * | 2012-08-30 | 2014-03-06 | 宝山钢铁股份有限公司 | High magnetic induction oriented silicon steel and manufacturing method thereof |
| CN103805918A (en) * | 2012-11-15 | 2014-05-21 | 宝山钢铁股份有限公司 | High-magnetic induction oriented silicon steel and production method thereof |
| CN109112283A (en) * | 2018-08-24 | 2019-01-01 | 武汉钢铁有限公司 | The preparation method of low temperature high magnetic induction grain-oriented silicon steel |
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| KR19990051483A (en) * | 1997-12-19 | 1999-07-05 | 이구택 | Manufacturing method of high magnetic flux density oriented electrical steel sheet by low temperature slab heating method |
| US20120000262A1 (en) * | 2008-12-31 | 2012-01-05 | Baoshan Iron & Steel Co., Ltd. | Method for manufacturing grain-oriented silicon steel with single cold rolling |
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