CN113502433A - Thin non-oriented silicon steel 35BW440 and production method thereof - Google Patents
Thin non-oriented silicon steel 35BW440 and production method thereof Download PDFInfo
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Abstract
The invention relates to thin non-oriented silicon steel 35BW440, wherein the non-oriented silicon steel 35BW440 comprises the following elements in percentage by mass: c: less than or equal to 0.003 percent, Si: 0.8% -2.0%, Mn: 0.4% -1.2%, P: less than or equal to 0.015 percent, S: less than or equal to 0.003 percent, Als: 0.25% -0.6%, N: less than or equal to 0.003 percent, Sb: 0.04% -0.1%, O: less than or equal to 0.0025 percent, and the balance of Fe and inevitable impurities. On the premise that the magnetic induction intensity of the non-oriented silicon steel is not increased by an electromagnetic stirring device, the {110} and {100} texture components which are beneficial to the electromagnetic performance are increased by adding Sb element, the electromagnetic performance is improved, and the surface quality of the non-oriented silicon steel is improved by adopting the processes of secondary cold rolling and intermediate continuous annealing.
Description
Technical Field
The invention relates to the technical field of alloy smelting, in particular to thin non-oriented silicon steel 35BW440 and a production method thereof.
Background
The non-oriented silicon steel is a silicon-iron alloy with very low carbon content, crystal grains of the non-oriented silicon steel are distributed in a random orientation mode in a deformed and annealed steel plate, the product is usually a cold-rolled plate or strip, the nominal thickness of the product is 0.35mm and 0.5mm, the non-oriented silicon steel is mainly used for manufacturing a motor and a generator, the magnetic induction intensity of the non-oriented silicon steel is high, a silicon steel sheet with higher magnetic induction can be obtained under the same magnetic field, the volume and the weight of a motor or a transformer iron core manufactured by the non-oriented silicon steel are smaller, and the silicon steel sheet, the copper wire, an insulating material and the like can be relatively saved.
In the prior art, argon is generally used for sealing and electromagnetic stirring during continuous casting to improve the magnetic induction intensity of non-oriented silicon steel, and the hot-rolled coil is finally subjected to normalizing annealing, wherein the normalizing annealing has the function of improving the grain structure of the hot-rolled coil, but electromagnetic stirring equipment and normalizing annealing equipment are not available on production lines of certain steel mills.
Therefore, it is necessary to develop a thin non-oriented silicon steel 35BW440 and a production method thereof, which can produce the non-oriented silicon steel with high magnetic induction strength without using electromagnetic stirring equipment and normalizing annealing equipment.
Disclosure of Invention
The present invention is directed to solving one of the technical problems of the prior art or the related art.
Therefore, the invention provides thin non-oriented silicon steel 35BW440 and a production method thereof.
In view of the above, in one aspect, the present invention provides a thin non-oriented silicon steel 35BW440, where the non-oriented silicon steel 35BW440 includes the following elements by mass:
c: less than or equal to 0.003 percent, Si: 0.8% -2.0%, Mn: 0.4% -1.2%, P: less than or equal to 0.015 percent, S: less than or equal to 0.003 percent, Als: 0.25% -0.6%, N: less than or equal to 0.003 percent, Sb: 0.04% -0.1%, O: less than or equal to 0.0025 percent, and the balance of Fe and inevitable impurities.
Further, the thickness of the thin gauge non-oriented silicon steel 35BW440 is 3.5 mm.
Further, the thin non-oriented silicon steel 35BW440 has an iron loss of 2.6W/kg to 3.1W/kg, a magnetic induction of 1.66T to 1.70T, a tensile strength of 380MPa to 400MPa, a yield strength of 420MPa to 450MPa, and an elongation of 35% to 42%.
In another aspect, the invention provides a production method for producing thin non-oriented silicon steel 35BW440, which comprises the following steps:
continuously casting into a plate blank;
carrying out hot continuous rolling on the plate blank to obtain a hot rolled plate;
carrying out primary cold rolling on the hot rolled plate to obtain a primary cold rolled plate;
carrying out intermediate continuous annealing treatment or cover annealing treatment on the primary cold-rolled sheet, and then carrying out secondary cold rolling to obtain a secondary cold-rolled sheet;
and carrying out final annealing treatment on the secondary cold-rolled sheet.
Further, the continuous casting into a slab includes:
the continuous casting adopts low superheat degree casting, the superheat degree is 18 ℃, the temperature of tundish molten steel is 1538 ℃, and the casting blank drawing speed is 0.8 m/min.
Further, the step of obtaining a hot-rolled plate after the hot continuous rolling of the slab comprises:
and (2) carrying out hot continuous rolling on a 1700mm hot rolling unit, wherein the thickness of the casting blank is 230mm, the thickness of the hot rolled steel plate is 2.55mm, the slab is subjected to a low-temperature heating process, the inlet temperature of the hot continuous rolling is not lower than 950 ℃, the final rolling temperature is 880 +/-15 ℃, and the coiling temperature is 700 +/-15 ℃.
Further, the heating temperature of the low-temperature heating process is not higher than 1100 ℃.
Further, the thickness of the primary cold-rolled plate is 0.7mm, and the thickness of the secondary cold-rolled plate is 0.35 mm.
Further, the annealing temperature of the intermediate continuous annealing is 940 ℃, and the annealing speed is 70m/min to 90 m/min.
Further, the final annealing includes: the temperature of a preheating section (NOF) is 980-1070 ℃, the temperature of a radiant tube heating section (RTF) is 920-970 ℃, the temperature of a soaking Section (SF) is 910-940 ℃, and the annealing speed is 70-90 m/min.
The technical scheme provided by the embodiment of the invention can have the following beneficial effects:
on the premise that the magnetic induction intensity of the non-oriented silicon steel is not increased by an electromagnetic stirring device, the {110} and {100} texture components which are beneficial to the electromagnetic performance are increased by adding Sb element, the electromagnetic performance is improved, and the surface quality of the non-oriented silicon steel is improved by adopting the processes of secondary cold rolling and intermediate continuous annealing.
It is to be understood that both the foregoing general description and the following detailed description are exemplary and explanatory only and are not restrictive of the invention, as claimed.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the invention and together with the description, serve to explain the principles of the invention.
In order to more clearly illustrate the embodiments or technical solutions in the prior art of the present invention, the drawings used in the description of the embodiments or prior art will be briefly described below, and it is obvious for those skilled in the art that other drawings can be obtained based on these drawings without creative efforts.
FIG. 1 shows a schematic flow chart of a method for producing thin gauge non-oriented silicon steel 35BW440 according to one embodiment of the present invention;
figure 2a shows the surface quality of thin gauge non-oriented silicon steel 35BW440 according to one embodiment of the present invention;
figure 2b shows the surface quality of a prior art thin gauge non-oriented silicon steel 50BW 470.
Detailed Description
Reference will now be made in detail to the exemplary embodiments, examples of which are illustrated in the accompanying drawings. When the following description refers to the accompanying drawings, like numbers in different drawings represent the same or similar elements unless otherwise indicated. The embodiments described in the following exemplary embodiments do not represent all embodiments consistent with the present invention. Rather, they are merely examples of apparatus and methods consistent with certain aspects of the invention, as detailed in the appended claims.
Example 1
The embodiment provides a thin non-oriented silicon steel 35BW440, wherein the non-oriented silicon steel 35BW440 comprises the following elements in percentage by mass:
c: less than or equal to 0.003 percent, Si: 0.8% -2.0%, Mn: 0.4% -1.2%, P: less than or equal to 0.015 percent, S: less than or equal to 0.003 percent, Als: 0.25% -0.6%, N: less than or equal to 0.003 percent, Sb: 0.04% -0.1%, O: less than or equal to 0.0025 percent, and the balance of Fe and inevitable impurities.
On the premise that the magnetic induction intensity of the non-oriented silicon steel is not increased by an electromagnetic stirring device, Sb elements are added, texture components of {110} and {100} which are beneficial to electromagnetic performance are added, the electromagnetic performance is improved, specifically, the Sb elements are segregated near a crystal boundary, the formation of the texture components of {100} and {110} which are beneficial to the electromagnetic performance is improved, the magnetic induction of the non-oriented silicon steel is improved, and meanwhile, the iron loss value is reduced.
Furthermore, the Sb element is added to improve the electromagnetic performance, so that the Si content can be properly reduced in the production process, and the influence of corrugation defects is reduced. Compared with other published production processes of high-grade non-oriented silicon steel, the production process does not adopt electromagnetic stirring equipment in the steel making process, and the Mn element is an austenite stabilizing element by adopting high Mn content, so that the phase transition temperature of austenite is increased, ferrite after gamma → alpha phase transition can be obviously refined, the generation of casting billet columnar crystals in the continuous casting process is reduced, and the surface corrugation defect of the non-oriented silicon steel under the high Si content is eliminated.
Further, the thickness of the thin gauge non-oriented silicon steel 35BW440 is 0.35 mm.
Further, the thin non-oriented silicon steel 35BW440 has an iron loss of 2.6W/kg to 3.1W/kg, a magnetic induction of 1.66T to 1.70T, a tensile strength of 380MPa to 400MPa, a yield strength of 420MPa to 450MPa, and an elongation of 35% to 42%.
The iron loss refers to the sum of hysteresis loss and eddy current loss (the residual loss can be ignored) of each unit mass of ferromagnetic materials in alternating and pulsating magnetic fields, and the production process increases the texture of favorable electromagnetic properties {110} and {100} through the grain boundary segregation action of Sb element, degrades the iron loss and improves the magnetic induction at the same time.
Example 2
Fig. 1 shows a flow chart of a method for producing thin gauge non-oriented silicon steel 35BW440 according to one embodiment of the invention.
As shown in fig. 1, the present embodiment provides a method for producing thin gauge non-oriented silicon steel 35BW440, which includes the following steps:
step 1, continuously casting into a plate blank;
step 2, carrying out hot continuous rolling on the plate blank to obtain a hot rolled plate;
step 3, carrying out primary cold rolling on the hot rolled plate to obtain a primary cold rolled plate;
step 4, after the primary cold-rolled sheet is subjected to intermediate continuous annealing treatment or cover annealing treatment, secondary cold rolling is carried out to obtain a secondary cold-rolled sheet;
and 5, carrying out final annealing treatment on the secondary cold-rolled sheet.
After the hot rolled sheet is obtained, it is necessary to perform a normalizing process on the hot rolled sheet to recrystallize coarse fibrous structures in the hot rolled coil, thereby improving the hot rolled structure and eliminating the influence of the corrugation defect.
The steel utilizes the existing equipment (without electromagnetic stirring equipment and normalizing annealing equipment), strengthens the control of steel-making chemical components, optimizes hot rolling and cold rolling production processes, adopts a secondary cold rolling intermediate annealing process, and improves the surface quality of the non-oriented silicon steel.
Specifically, under the condition of no electromagnetic stirring, Sb element is added through chemical design, the electromagnetic performance is improved through optimizing the texture structure of the product, the Si content is properly reduced, the influence of hot rolling coarse fiber structure is eliminated through a secondary cold rolling method, and the high-grade non-oriented silicon steel product without surface corrugation defects is obtained.
The comparison between the non-oriented silicon steel 35BW440 produced by the secondary cold rolling method and the standard parameters is shown in Table 1:
table 1: comparison table of non-oriented silicon steel 35BW440 and existing standard parameters
As can be seen from Table 1, by the production method and the chemical elements, the electromagnetic performance of the 35BW440 non-oriented silicon steel is improved by adding the Sb element and combining a secondary cold rolling method on the premise of no electromagnetic stirring equipment, and the thin non-oriented silicon steel meeting the standard can also be produced.
Wherein the continuous casting into the slab comprises:
the continuous casting adopts low superheat degree casting, the superheat degree is 18 ℃, the temperature of tundish molten steel is 1538 ℃, and the casting blank drawing speed is 0.8 m/min.
Further, the step of obtaining the hot-rolled plate after the hot continuous rolling of the slab comprises:
and (2) carrying out hot continuous rolling on a 1700mm hot rolling unit, wherein the thickness of a casting blank is 230mm, the thickness of a hot rolled steel plate is 2.55mm, the plate blank adopts a low-temperature heating process, the inlet temperature of the hot continuous rolling is not lower than 950 ℃, the final rolling temperature is 880 +/-15 ℃, and the coiling temperature is 700 +/-15 ℃.
The hot rolling high-temperature finish rolling and the high-temperature coiling are beneficial to the exertion of the grain boundary segregation effect of the Sb element, and further the magnetic induction intensity of the non-oriented silicon steel is improved.
Further, the heating temperature of the low-temperature heating process is not higher than 1100 ℃.
Further, the thickness of the primary cold-rolled plate was 0.7mm, and the thickness of the secondary cold-rolled plate was 0.35 mm.
It should be noted that the thickness of the non-oriented silicon steel with various specifications is fixed, and needs to be set according to the user requirement, and 35BW440 is taken as an example in this embodiment.
Further, the annealing temperature of the intermediate continuous annealing is 940 ℃, and the annealing speed is 70m/min to 90 m/min.
After the secondary cold rolling, the structure performance of the hot-rolled steel plate can be improved by intermediate annealing (or cover annealing), so that crystal grains grow uniformly, the texture structure beneficial to the electromagnetic performance in the hot-rolled steel plate is increased, and the electromagnetic performance of a final product is improved.
Further, the final annealing includes: the temperature of a preheating section (NOF) is 980-1070 ℃, the temperature of a radiant tube heating section (RTF) is 920-970 ℃, the temperature of a soaking Section (SF) is 910-940 ℃, and the annealing speed is 70-90 m/min.
The final annealing belongs to high-temperature low-speed annealing, and the process is favorable for exerting the grain boundary segregation function of the Sb element, so that the Sb element is segregated at the grain boundary, the {110} and {100} oriented textures favorable for electromagnetic performance are increased, the {111} oriented texture is reduced, and the electromagnetic performance of a final product is improved.
Comparative example
Figure 2a shows the surface quality of thin gauge non-oriented silicon steel 35BW440 according to one embodiment of the present invention; figure 2b shows the surface quality of a prior art thin gauge non-oriented silicon steel 50BW 470.
As shown in fig. 2a and 2b, on the premise that Sb element is added and Si content is correspondingly reduced, after the processing method of secondary cold rolling and continuous annealing, the surface quality of the non-oriented silicon steel 35BW440 is better and no corrugation defect occurs on the premise that the basic performance of the thin non-oriented silicon steel is ensured.
Other embodiments of the invention will be apparent to those skilled in the art from consideration of the specification and practice of the invention disclosed herein. This application is intended to cover any variations, uses, or adaptations of the invention following, in general, the principles of the invention and including such departures from the present disclosure as come within known or customary practice within the art to which the invention pertains. It is intended that the specification and examples be considered as exemplary only, with a true scope and spirit of the invention being indicated by the following claims.
It is to be understood that the present invention is not limited to what has been described above, and that various modifications and changes may be made without departing from the scope thereof. The scope of the invention is limited only by the appended claims.
Claims (10)
1. The thin-gauge non-oriented silicon steel 35BW440, wherein the non-oriented silicon steel 35BW440 comprises the following elements in percentage by mass:
c: less than or equal to 0.003 percent, Si: 0.8% -2.0%, Mn: 0.4% -1.2%, P: less than or equal to 0.015 percent, S: less than or equal to 0.003 percent, Als: 0.25% -0.6%, N: less than or equal to 0.003 percent, Sb: 0.04% -0.1%, O: less than or equal to 0.0025 percent, and the balance of Fe and inevitable impurities.
2. The thin gauge non-oriented silicon steel 35BW440 of claim 1, wherein the thin gauge non-oriented silicon steel 35BW440 has a thickness of 0.35 mm.
3. The thin gauge non-oriented silicon steel 35BW440 of claim 1, wherein the thin gauge non-oriented silicon steel 35BW440 has an iron loss of 2.6W/kg to 3.1W/kg, a magnetic induction of 1.66T to 1.70T, a tensile strength of 380MPa to 400MPa, a yield strength of 420MPa to 450MPa, and an elongation of 35% to 42%.
4. A production method for producing the thin gauge non-oriented silicon steel 35BW440 of any one of claims 1 to 3, wherein the production method comprises the following steps:
continuously casting into a plate blank;
carrying out hot continuous rolling on the plate blank to obtain a hot rolled plate;
carrying out primary cold rolling on the hot rolled plate to obtain a primary cold rolled plate;
carrying out intermediate continuous annealing treatment or cover annealing treatment on the primary cold-rolled sheet, and then carrying out secondary cold rolling to obtain a secondary cold-rolled sheet;
and carrying out final annealing treatment on the secondary cold-rolled sheet.
5. The method of producing thin gauge non-oriented silicon steel 35BW440 of claim 4, wherein the continuously casting into slabs comprises:
the continuous casting adopts low superheat degree casting, the superheat degree is 18 ℃, the temperature of tundish molten steel is 1538 ℃, and the casting blank drawing speed is 0.8 m/min.
6. The method of producing the thin gauge non-oriented silicon steel 35BW440 of claim 4, wherein the obtaining of the hot rolled plate after the hot continuous rolling of the slab comprises:
and (2) carrying out hot continuous rolling on a 1700mm hot rolling unit, wherein the thickness of the casting blank is 230mm, the thickness of the hot rolled steel plate is 2.55mm, the slab is subjected to a low-temperature heating process, the inlet temperature of the hot continuous rolling is not lower than 950 ℃, the final rolling temperature is 880 +/-15 ℃, and the coiling temperature is 700 +/-15 ℃.
7. The method of producing the thin gauge non-oriented silicon steel 35BW440 of claim 6, wherein the low temperature heating process is performed at a temperature of not higher than 1100 ℃.
8. The method of producing the thin gauge non-oriented silicon steel 35BW440 of claim 4, wherein the thickness of the primary cold rolled plate is 0.7mm, and the thickness of the secondary cold rolled plate is 0.35 mm.
9. The method of producing the thin gauge non-oriented silicon steel 35BW440 of claim 4, wherein the annealing temperature of the intermediate continuous annealing is 940 ℃ and the annealing speed is 70m/min to 90 m/min.
10. The method of producing thin gauge non-oriented silicon steel 35BW440 of claim 4, wherein the final annealing comprises: the temperature of a preheating section (NOF) is 980-1070 ℃, the temperature of a radiant tube heating section (RTF) is 920-970 ℃, the temperature of a soaking Section (SF) is 910-940 ℃, and the annealing speed is 70-90 m/min.
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Cited By (4)
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| CN114250420A (en) * | 2021-12-30 | 2022-03-29 | 本钢板材股份有限公司 | Production method of cover type intermediate annealing high-grade non-oriented silicon steel 50BW350 |
| CN116240471A (en) * | 2023-02-21 | 2023-06-09 | 包头钢铁（集团）有限责任公司 | Sb-containing non-oriented silicon steel 50W600 and preparation method thereof |
| CN117947249A (en) * | 2024-03-26 | 2024-04-30 | 包头威丰新材料有限公司 | Process for relieving brittle failure of low-temperature high-magnetic-induction oriented silicon steel strip |
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