CN114045433B - Ultra-low iron loss non-oriented silicon steel and production method thereof - Google Patents
Ultra-low iron loss non-oriented silicon steel and production method thereof Download PDFInfo
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- C21D1/26—Methods of annealing
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- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Abstract
The invention discloses an ultra-low iron loss non-oriented silicon steel and a production method thereof, wherein the production method comprises the following steps: molten iron desulfurization, converter smelting and RH furnace refining are sequentially adopted for smelting steel, and the finally obtained molten steel comprises the following chemical components in percentage by mass: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of S, less than or equal to 0.0015 percent of N, less than or equal to 0.0020 percent of N, less than or equal to 0.03 percent of P, less than or equal to 0.003 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent or more and less than or equal to 4.15 percent of Si and Al, and the balance of Fe and inevitable impurities; continuously casting molten steel obtained by smelting into a continuous casting billet; heating the continuous casting billet and then performing multi-pass rolling to obtain a hot-rolled coil; shearing the two side edges of the hot-rolled coil; normalizing and acid-washing, wherein the normalizing temperature is 900-930 ℃, and the normalizing time is 30-60 s; the non-oriented silicon steel with the thickness of 0.35-0.5 mm is obtained through multi-pass cold rolling, wherein the reduction rate in the first cold rolling is more than or equal to 37 percent, and the rolling speed is 70-180 m/min. The non-oriented silicon steel prepared by the invention has ultralow iron loss and is not easy to break strips during cold rolling.
Description
Technical Field
The invention belongs to the technical field of steel smelting, relates to a production method of ultralow-iron-loss non-oriented silicon steel, and further relates to ultralow-iron-loss non-oriented silicon steel prepared by the production method.
Background
Non-oriented silicon steel is widely used as a core material for motors and transformers, and thus is required to have good magnetic properties, including lower core loss and higher magnetic induction. In recent years, with the continuous improvement of the energy efficiency of a motor and the enhancement of energy-saving and environment-friendly consciousness, the requirement on the efficiency of an electric appliance is higher and higher, and one measure for improving the efficiency of the electric appliance is to improve the magnetic property of an iron core material and prepare non-oriented silicon steel with lower iron loss.
In order to obtain the non-oriented silicon steel with lower iron loss, the content of silicon and aluminum alloy elements in the high-grade non-oriented silicon steel is continuously improved. However, with the increase of the content of silicon and aluminum alloy elements, the toughness of the steel strip is sharply reduced and the brittleness is increased, so that strip breakage accidents are easily caused in the cold rolling process, and the rolling efficiency and the yield of the cold rolling are influenced.
In the production process of the existing ultra-low iron loss non-oriented silicon steel, in order to reduce the strip breakage rate during rolling, a heating system is usually added before rolling to increase the temperature of a rolled piece and increase the plasticity of the rolled piece, however, the heating equipment in the mode has high investment, high energy consumption and greatly increased cost.
Disclosure of Invention
The invention aims to provide ultralow-iron-loss non-oriented silicon steel and a production method thereof, and aims to solve the technical problems of high cold-rolling strip breakage rate and low yield in the preparation of the low-iron-loss non-oriented silicon steel in the prior art.
In order to accomplish one of the above objects, an embodiment of the present invention provides a method for producing a high-grade non-oriented silicon steel, comprising the steps of,
smelting: molten iron desulfurization, converter smelting and RH furnace refining are sequentially adopted for smelting steel, and the finally obtained molten steel comprises the following chemical components in percentage by mass: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of S, less than or equal to 0.0015 percent of N, less than or equal to 0.0020 percent of N, less than or equal to 0.03 percent of P, less than or equal to 0.003 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent or more and less than or equal to 4.15 percent of Si and Al, and the balance of Fe and inevitable impurities;
continuous casting: continuously casting the molten steel obtained by smelting into a continuous casting billet;
hot rolling: heating the continuous casting billet and then performing multi-pass rolling to obtain a hot-rolled coil;
trimming: shearing the two side edges of the hot-rolled coil;
normalized acid washing: the normalizing temperature is 900-930 ℃, and the normalizing time is 30-60 s;
cold rolling: the non-oriented silicon steel with the thickness of 0.35-0.5 mm is obtained through multi-pass cold rolling, wherein the reduction rate in the first cold rolling is more than or equal to 37 percent, and the rolling speed is 70-180 m/min.
Preferably, in the smelting process, the molten steel finally obtained comprises the following chemical components in percentage by mass: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of S, less than or equal to 0.0010 percent of N, less than or equal to 0.0015 percent of P, less than or equal to 0.03 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent or more of Si and Al, less than or equal to 4.15 percent, and the balance of Fe and inevitable impurities.
Preferably, in the hot rolling step, the thickness of the hot rolled coil prepared is 1.9 to 2.3mm, the difference between the thicknesses of the middle part and the side part of the hot rolled coil is 20 to 40 μm, and the difference between the thicknesses of the two side parts of the hot rolled coil is less than or equal to 22 μm.
Preferably, in the hot rolling procedure, the obtained continuous casting slab is heated to 1080-1130 ℃ and kept for 30-50 min.
Preferably, in the hot rolling step, the finish rolling temperature of the hot rolling is 830 to 870 ℃, and the coiling temperature is 620 to 680 ℃.
Preferably, in the edge cutting process, the shearing width of one side is more than or equal to 20mm.
Preferably, the average grain diameter of the normalized steel strip is 130 to 150 μm.
Preferably, the production method further comprises: annealing the cold-hard steel coil obtained by cold rolling by adopting a continuous annealing furnace to obtain a finished product, wherein the annealing temperature of the finished product is 950-1000 ℃, and the annealing time is 20-30 s; and cooling, coating and finishing the annealed steel strip to obtain a finished product of the non-oriented silicon steel.
In order to achieve the above purpose, an embodiment of the present invention further provides an ultra-low iron loss non-oriented silicon steel, which is prepared by the above production method.
Preferably, the thickness of the finished product of the ultra-low iron loss non-oriented silicon steel is 0.5mm, and the iron loss P of the finished product of the ultra-low iron loss non-oriented silicon steel 1.5/50 Not more than 2.35W/kg, and magnetic induction intensity B 5000 Not less than 1.66T; or the thickness of the finished product of the ultra-low iron loss non-oriented silicon steel is 0.35mm, and the iron loss P of the finished product is 1.5/50 Less than or equal to 2.10W/kg, magnetic induction intensity B 5000 ≥1.65T。
Compared with the prior art, the invention has the following beneficial effects:
(1) In the aspect of chemical composition design, the iron loss can be reduced to the maximum extent by increasing the contents of Si and Al, the probability of precipitating fine MnS and AlN in a hot rolling procedure is reduced by matching with the control of the contents of elements such as S, N and the like, the magnetic property is ensured by combining the control of the contents of the elements such as N, ti, V and Nb, and the low iron loss and the high magnetic induction strength are realized.
(2) By means of the component proportion and the combination of process design, the prepared non-oriented silicon steel has uniform structure, lower iron loss and excellent magnetic induction performance, the application energy efficiency of the non-oriented silicon steel in products such as motors and transformers is met, the toughness of the prepared non-oriented silicon steel is improved by optimizing processing technologies such as hot rolling, trimming, normalizing, cold rolling and the like, frequent strip breakage caused by high brittleness of the silicon steel in the cold rolling process is avoided, the rolling efficiency and the production yield of the non-oriented silicon steel are greatly improved, and the production cost is reduced.
(3) Through the design of the chemical components of the non-oriented silicon steel, the low-temperature rolling and the high-temperature coiling of the hot rolling process are combined, and the heating temperature and the heating duration of a continuous casting billet are controlled, so that the production efficiency is ensured, the high-temperature finish rolling of subsequent finish rolling is facilitated, the probability of precipitating fine MnS and AlN is reduced, the solid solution of precipitates such as MnS and AlN in the steel in the heating process is prevented, the growth of tissue grains is facilitated, and further the subsequently prepared non-oriented silicon steel finished product has excellent magnetic performance; meanwhile, the finish rolling temperature of finish rolling is controlled in a high-temperature ferrite area, so that high-temperature ferrite is formed, and a deformed fiber structure is avoided.
(4) On the basis of the design of the chemical components of the non-oriented silicon steel, the edge of the hot-rolled coiled plate is cut off by trimming the hot-rolled coiled plate before normalization, and an abrupt thickness reduction area of the edge of the steel plate caused by hot rolling is cut off, wherein the abrupt thickness reduction area refers to an area with large variation of the thickness of the edge of the steel plate, so that the large difference of the deformation degree of the edge of the steel plate and the middle part during cold rolling is avoided, the control of the plate shape is facilitated, the expansion of edge cracks during the cold rolling process is effectively avoided, the phenomenon that the toughness of the two side edges of the hot-rolled coiled plate is changed into brittleness after normalization is avoided, the edge quality of the hot-rolled coiled plate after trimming is ensured, the edge damage and edge cracking during the cold rolling process are reduced, the shearing stress generated by trimming can be released after normalization, the stress concentration of the two side edges of the steel plate during the cold rolling process is reduced, the internal reason for causing the cold rolling edge cracking is eradicated, and the internal cracks of the cold-rolled edge are completely eliminated.
(5) Further through the normalizing process, the structure and product magnetism of the non-oriented silicon steel hot-rolled steel plate can be improved, the hot-rolled coil structure is more uniform, the components of favorable textures (100) and (110) are improved, the components of unfavorable textures (111) are weakened, the condition that the head, middle and tail magnetic properties are inconsistent is improved, further on the basis of the chemical components of the non-oriented silicon steel, the grain growth in the non-oriented silicon steel with high alloy content is facilitated through controlling the normalizing temperature and time, and therefore the average grain size of the steel strip subjected to the normalizing annealing is controlled to be 130-150 mu m, the toughness of the steel strip is maintained, and the risk of strip breakage during cold rolling is reduced.
(6) The cold rolling process and parameter setting are further combined, the deformation of the edge of the steel strip can be increased, the edge crack trend of the edge of the steel strip can be reduced, the deformation heat of the steel strip can be increased by large reduction rate, the rolling temperature of the steel strip is improved, coarse grains are crushed, the grains are refined, the toughness and plasticity of the steel strip are improved, and the rolling yield is improved. The control of the rolling speed of the first pass of cold rolling is combined, so that the stable and smooth operation of the cold rolling process is facilitated, the strip breakage risk in the rolling process is reduced, and the high-temperature effect of the steel strip caused by heat generation in processing is improved.
Drawings
FIG. 1 is a photomicrograph of the metallographic structure of the steel strip edge of example 7 of the present invention;
FIG. 2 is a photomicrograph of the metallographic structure of the steel strip edge of example 8 of the present invention;
FIG. 3 is a photomicrograph of the metallographic structure of the steel strip of comparative example 17 of the present invention;
FIG. 4 is a photomicrograph of the microstructure of the steel strip edge of comparative example 18 of the present invention.
Detailed Description
The present invention will be described in detail below with reference to specific embodiments shown in the drawings. These embodiments are not intended to limit the present invention, and structural, methodological, or functional changes made by those skilled in the art according to these embodiments are included in the scope of the present invention.
The invention provides a production method of ultra-low iron loss non-oriented silicon steel and the ultra-low iron loss non-oriented silicon steel prepared by the production method.
The production method of the ultra-low iron loss non-oriented silicon steel is specifically described below, and comprises the working procedures of smelting, continuous casting, hot rolling, trimming, normalized pickling, cold rolling, annealing, cooling, coating, finishing and the like which are sequentially carried out.
In the embodiment, the chemical composition design scheme of the ultra-low iron loss non-oriented silicon steel is as follows, and the chemical compositions in percentage by mass are as follows: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of S, less than or equal to 0.0015 percent of N, less than or equal to 0.0020 percent of N, less than or equal to 0.03 percent of P, less than or equal to 0.003 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent or more and less than or equal to 4.15 percent of Si and Al, and the balance of Fe and inevitable impurities.
The effects of the elements in the chemical composition design of the ultra-low iron loss non-oriented silicon steel are explained below.
C: in non-oriented silicon steel, it is generally considered that C is a harmful element, and an increase in C content causes fine crystal grains in the finished product, high iron loss, a problem of magnetic aging, and deterioration of magnetic characteristics, so in the present embodiment, the C content (in terms of mass%) is controlled to be not more than 0.003%.
Si: the Si content (in mass%) is controlled to 2.8 to 3.4% in the present embodiment because the Si content is an element that increases the resistivity of the electromagnetic steel sheet, and can effectively reduce the iron loss and increase the strength of the steel strip, but too much Si content causes embrittlement of the steel strip and significantly increases the risk of breakage during rolling.
Mn: mn is easy to react with S to generate MnS, which is beneficial to reducing S dissolved in hot rolling plate blank during heating, and proper Mn is added to inhibit hot brittleness caused by S; in the present embodiment, the Mn content (in mass%) is controlled to 0.1 to 0.5%.
Al: the magnetic steel sheet is also an effective additive element for improving the electrical resistivity of the electromagnetic steel sheet and reducing the iron loss, and the magnetic induction intensity can be reduced due to the excessively high content of the magnetic steel sheet, the brittleness of the steel sheet is greatly increased, and the processing difficulty of cold rolling and the like is increased; the lower content thereof causes a decrease in resistivity, and nitrides such as AlN are finely precipitated to deteriorate grain growth and increase iron loss, and in the present embodiment, the content (in mass%) of Al is controlled to 0.6 to 1.3%. Meanwhile, si + Al is controlled to be more than or equal to 3.80% and less than or equal to 4.15%, so that high resistivity, low iron loss and steel plate brittleness are considered, and the processing difficulty of cold rolling and other working procedures is avoided.
S: the Mn-S alloy is a harmful element and is an important component element of inclusions in steel, particularly MnS precipitates in the steel are subjected to mass solid solution when the steel is heated before a billet is subjected to hot rolling, and then dispersed and precipitated in the hot working process, so that the growth of crystal grains in the annealing process of a finished product is prevented, the magnetism of the finished product is reduced, the magnetic induction intensity is reduced and the iron loss is increased due to the increase of the content of the MnS precipitates, and in the embodiment, the content of S (calculated by mass percent) is controlled to be less than or equal to 0.0015 percent in order to avoid the precipitation of fine MnS in the hot rolling process.
N: the AlN is also an important component element of inclusions in steel, and AlN formed in a steel billet can be greatly dissolved in a solid solution in the hot rolling and heating process and then dispersed and precipitated in the hot processing process to prevent the growth of crystal grains in the annealing process of a finished product and reduce the magnetism of the finished product, so the content of N (calculated by mass percent) is controlled to be less than or equal to 0.0020 percent.
P: the iron loss can be effectively improved, the strength of the steel strip can be effectively improved and the punching performance can be improved by increasing the content of the P, but the cold ductility of the steel can be obviously deteriorated by excessively increasing the content of the P, so that the content of the P (calculated by mass percent) is controlled to be less than or equal to 0.03 percent.
Ti: because the Al content in the chemical components is high, tiO in slag is reduced by Al when alloy is added in the refining process, ti enters molten steel again to increase the Ti content in the steel, but Ti is used as a forming element of carbide and nitride in the steel, and fine precipitates of the Ti can hinder the growth of finished product crystal grains in the annealing process, deteriorate the magnetic performance of non-oriented silicon steel, and cause the increase of iron loss and the reduction of magnetic induction intensity, so that the Ti content (by mass percent) is controlled to be less than or equal to 0.003 percent.
V, nb: v and Nb are used as carbide and nitride forming elements and are main impurity elements, and the content of both is controlled to be not more than 0.003%.
In the aspect of chemical composition design, the iron loss can be reduced to the maximum extent by increasing the contents of Si and Al, the probability of precipitating fine MnS and AlN in a hot rolling procedure is reduced by matching with the control of the contents of elements such as S, N and the like, and the magnetic property is ensured by combining the control of the contents of the elements such as N, ti, V and Nb, so that the low iron loss and the high magnetic induction strength are realized.
Specifically, the method for producing the ultra-low iron loss non-oriented silicon steel of the present embodiment includes the following steps.
(1) Smelting of
Molten iron desulfurization, converter smelting and RH furnace refining are sequentially adopted to smelt steel according to the chemical components, namely, the chemical components of the finally obtained molten steel are calculated by mass percent: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of the total weight of the alloy, less than or equal to 0.0015 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.03 percent of P, less than or equal to 0.003 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent to 4.15 percent of Si + Al, and the balance of Fe and inevitable impurities.
The specific operations of the molten iron desulphurization, converter smelting and RH furnace refining processes can be realized by adopting the existing corresponding technology, and are not described in more detail.
Preferably, the chemical components of the finally obtained molten steel are as follows by mass percent: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of S, less than or equal to 0.0010 percent of N, less than or equal to 0.0015 percent of P, less than or equal to 0.03 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent or more of Si and Al, less than or equal to 4.15 percent, and the balance of Fe and inevitable impurities. Therefore, the method is more beneficial to the growth of crystal grains in the annealing process of the finished product, improves the magnetic property of the product, reduces the number of inclusions in the product and reduces the size of the inclusions.
(2) Continuous casting
Specifically, after tapping molten steel obtained by refining in an RH furnace, continuous casting equipment is adopted to prepare a continuous casting billet with the thickness of 210-230 mm, and the continuous casting process can be realized by adopting the existing feasible continuous casting technology, and is not described again.
(3) Hot rolling
And (3) heating, multi-pass rough rolling, multi-pass finish rolling, cooling and coiling the continuous casting billet obtained in the continuous casting process in sequence to prepare the hot-rolled coil.
Preferably, the thickness of the prepared hot-rolled coil plate is controlled to be 1.9-2.3 mm, the difference between the thicknesses of the middle part and the edge part of the hot-rolled coil plate is controlled to be 20-40 mu m, and the difference between the thicknesses of the two edge parts of the hot-rolled coil plate is controlled to be less than or equal to 22 mu m. Thus, the thickness of the hot-rolled coil is controlled to be 1.9-2.3 mm, which is beneficial to the formation of textures (100) and (110) and the control of hot-rolled plate shape, and the uneven rolling pressure between the middle part and the two side parts of the hot-rolled coil and the uneven rolling pressure between the two side parts can be reduced by controlling the thickness difference between the middle part and the side parts of the hot-rolled steel plate and the thickness difference between the two side parts, thereby effectively reducing the side cracks and the side damage.
Preferably, in the hot rolling process, the continuous casting slab obtained in the continuous casting process is heated to 1080-1130 ℃ and is kept warm for 30-50 min, and then is subjected to multi-pass rough rolling, multi-pass finish rolling, cooling and coiling to prepare a hot rolled coil with the thickness of 1.9-2.3 mm.
Wherein the finish rolling temperature of the finish rolling is 830-870 ℃, and the coiling temperature is 620-680 ℃.
Thus, on the basis of the design of the chemical components, the low-temperature rolling and the high-temperature coiling of the hot rolling process are combined, and the heating temperature and the heating duration of the continuous casting billet are controlled, so that the production efficiency is ensured, the high-temperature finish rolling of subsequent finish rolling is facilitated, the probability of precipitating fine MnS and AlN is reduced, the solid solution of precipitates such as MnS and AlN in the steel in the heating process is prevented, the growth of tissue grains is facilitated, and the subsequently prepared non-oriented silicon steel finished product has excellent magnetic performance; meanwhile, the finish rolling temperature of finish rolling is controlled in a high-temperature ferrite area, so that high-temperature ferrite is formed, and a deformed fiber structure is avoided.
(4) Edge cutting
And shearing the two side edges of the hot-rolled coil by using a circle shear.
Wherein the shearing width of one side is more than or equal to 20mm.
On the basis of the chemical composition design, through the trimming process, not only are edge defects of the hot-rolled coil cut off, and a thickness steep drop zone of the edge of the steel plate caused by hot rolling is cut off, wherein the steep drop zone refers to a zone with a large change in the thickness of the edge of the steel plate, so that the large difference of the deformation degree of the edge and the middle part of the steel plate during cold rolling is avoided, the control of the shape of the plate is facilitated, the expansion of edge cracks in the cold rolling process is effectively avoided, the phenomenon that the two side edges of the hot-rolled coil change from toughness to brittleness after normalization is avoided, the edge quality of the hot-rolled coil after trimming is ensured, the edge damage and edge cracking in the cold rolling process are reduced, the shearing stress generated by trimming can be released after normalization, the stress concentration of the two side edges of the steel plate during the cold rolling process is reduced, the inherent reason for causing the cold-rolled edge cracking is eradicated, and the cold-rolled edge cracks are completely eliminated.
(5) Normalized acid washing
Normalizing and pickling the steel strip after the edge cutting.
The normalizing process is completed in a normalizing furnace, wherein the normalizing temperature is 900-930 ℃, and the normalizing time is 30-60 s;
the normalizing process can improve the structure and product magnetism of the non-oriented silicon steel hot rolled plate, so that the structure of the hot rolled plate is more uniform, components favorable for texture (100) and (110) are improved, components unfavorable for texture (111) are weakened, and the condition that the head-to-tail magnetic performance is inconsistent is improved.
(6) Cold rolling
And cold rolling the steel plate into non-oriented silicon steel with the thickness of 0.35-0.5 mm in multiple passes on a cold rolling line.
Wherein the reduction rate in the first cold rolling is more than or equal to 37 percent, and the rolling speed is 70-180 m/min.
The large reduction rate is adopted for the first cold rolling pass through control, so that the deformation of the edge of the steel strip can be increased, the edge crack trend of the edge of the steel strip is reduced, meanwhile, the deformation heat of the steel strip can be increased by the large reduction rate, the rolling temperature of the steel strip is improved, coarse grains are crushed, the grains are refined, the toughness and the plasticity of the steel strip are improved, and the rolling yield is improved. The control of the rolling speed of the first pass of cold rolling is combined, so that the stable and smooth operation of the cold rolling process is facilitated, the strip breakage risk in the rolling process is reduced, and the high-temperature effect of the steel strip caused by processing heating is improved.
Specifically, in the present embodiment, 4 passes of rolling are collectively used in the cold rolling step, and the steel strip is rolled from a thickness of 1.9 to 2.3mm to ultra-low iron loss non-oriented silicon steel with a thickness of 0.5mm, so as to meet the size requirement of high-grade non-oriented silicon steel. In other embodiments, the cold rolling process may also adopt 5 passes of rolling to roll the steel strip from a thickness of 1.9-2.3 mm to an ultra-low iron loss non-oriented silicon steel with a thickness of 0.35mm, so as to meet the size requirement of high-grade non-oriented silicon steel.
(7) Annealing the finished product
And annealing the cold-rolled hard steel coil by a continuous annealing furnace, wherein the annealing temperature of the finished product is 950-1000 ℃, and the annealing time is 20-30 s.
(8) Coating, finishing, roll-to-roll packaging
And cooling the annealed steel strip, coating an insulating layer on the surface of the finished product and finishing to obtain the non-oriented silicon steel finished product, so that the finished product has excellent insulating property.
The ultra-low iron loss non-oriented silicon steel provided by the embodiment of the invention is prepared by the production method, and comprises the following chemical components in percentage by mass: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of S, less than or equal to 0.0015 percent of N, less than or equal to 0.0020 percent of N, less than or equal to 0.03 percent of P, less than or equal to 0.003 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent or more and less than or equal to 4.15 percent of Si and Al, and the balance of Fe and inevitable impurities.
When the thickness of the ultra-low iron loss non-oriented silicon steel is 0.50mm, the iron loss P is 1.5/50 Not more than 2.35W/kg, and magnetic induction intensity B 5000 The rolling mill has the advantages that the rolling mill is more than or equal to 1.66T, the magnetic induction performance is excellent, the requirements of application energy efficiency of the rolling mill in products such as motors and transformers can be met, and the strip breakage rate in the rolling process is less than 2%.
When the thickness of the ultra-low iron loss non-oriented silicon steel is 0.35mm, the iron loss P of the silicon steel is 1.5/50 Less than or equal to 2.10W/kg, and magnetic induction intensity B 5000 The rolling process has the advantages that the rolling process is more than or equal to 1.65T, the magnetic induction performance is excellent, the requirements of application energy efficiency of the rolling process in products such as motors and transformers can be met, and the strip breakage rate in the rolling process is less than 2%.
Compared with the prior art, the invention has the beneficial effects that:
(1) In the aspect of chemical composition design, the iron loss can be reduced to the maximum extent by increasing the contents of Si and Al, the probability of precipitating fine MnS and AlN in a hot rolling procedure is reduced by matching with the control of the contents of elements such as S, N and the like, the magnetic performance is ensured by combining the control on the contents of the elements such as N, ti, V and Nb, and the low iron loss and the high magnetic induction strength are realized.
(2) By means of the component proportion and the combination of process design, the prepared non-oriented silicon steel has uniform structure, lower iron loss and excellent magnetic induction performance, the application energy efficiency of the non-oriented silicon steel in products such as motors and transformers is met, the toughness of the prepared non-oriented silicon steel is improved by optimizing processing technologies such as hot rolling, trimming, normalizing, cold rolling and the like, frequent strip breakage caused by high brittleness of the silicon steel in the cold rolling process is avoided, the rolling efficiency and the production yield of the non-oriented silicon steel are greatly improved, and the production cost is reduced.
(3) Through the design of the chemical components of the non-oriented silicon steel, the low-temperature rolling and the high-temperature coiling of the hot rolling process are combined, and the heating temperature and the heating duration of the continuous casting billet are controlled, so that the production efficiency is ensured, the high-temperature finish rolling of subsequent finish rolling is facilitated, the probability of separating out fine MnS and AlN is reduced, the solid solution of precipitates such as MnS and AlN in the steel in the heating process is prevented, the growth of tissue grains is facilitated, and further the subsequently prepared non-oriented silicon steel finished product has excellent magnetic performance; meanwhile, the finishing temperature of finish rolling is controlled in a high-temperature ferrite area, so that high-temperature ferrite is formed, and a deformed fiber structure is avoided.
(4) On the basis of the design of the chemical components of the non-oriented silicon steel, the edge of the hot-rolled coiled plate is cut off by trimming the hot-rolled coiled plate before normalization, and an abrupt thickness reduction area of the edge of the steel plate caused by hot rolling is cut off, wherein the abrupt thickness reduction area refers to an area with large variation of the thickness of the edge of the steel plate, so that the large difference of the deformation degree of the edge of the steel plate and the middle part during cold rolling is avoided, the control of the plate shape is facilitated, the expansion of edge cracks during the cold rolling process is effectively avoided, the phenomenon that the toughness of the two side edges of the hot-rolled coiled plate is changed into brittleness after normalization is avoided, the edge quality of the hot-rolled coiled plate after trimming is ensured, the edge damage and edge cracking during the cold rolling process are reduced, the shearing stress generated by trimming can be released after normalization, the stress concentration of the two side edges of the steel plate during the cold rolling process is reduced, the internal reason for causing the cold rolling edge cracking is eradicated, and the internal cracks of the cold-rolled edge are completely eliminated.
(5) Further through the normalizing process, the structure and product magnetism of the non-oriented silicon steel hot rolled steel plate can be improved, the structure of a hot rolled coil is more uniform, the components of favorable textures (100) and (110) are improved, the components of unfavorable textures (111) are weakened, the condition that the head-to-tail magnetic performance is inconsistent is improved, further on the basis of the chemical components of the non-oriented silicon steel, the grain growth in the non-oriented silicon steel with high alloy content is facilitated through controlling the normalizing temperature and time, and therefore the average grain size of the steel strip subjected to normalizing annealing is controlled to be 130-150 mu m, the toughness of the steel strip is maintained, and the strip breakage risk during cold rolling is reduced.
(6) The cold rolling process and parameter setting are further combined, the deformation of the edge of the steel strip can be increased, the edge crack trend of the edge of the steel strip can be reduced, the deformation heat of the steel strip can be increased by large reduction rate, the rolling temperature of the steel strip is improved, coarse grains are crushed, the grains are refined, the toughness and plasticity of the steel strip are improved, and the rolling yield is improved. The control of the rolling speed of the first pass of cold rolling is combined, so that the stable and smooth operation of the cold rolling process is facilitated, the strip breakage risk in the rolling process is reduced, and the high-temperature effect of the steel strip caused by heat generation in processing is improved.
The detailed description set forth above is merely a specific description of possible embodiments of the present invention and is not intended to limit the scope of the invention, which is intended to include within the scope of the invention equivalent embodiments or modifications that do not depart from the technical spirit of the present invention.
The advantages of the invention are further illustrated below by 6 examples and 10 comparative examples, of course, these 6 examples are only some, but not all, of the many variations that can be included in the invention. 6 examples and 10 comparative examples each provide a non-oriented silicon steel, and the production method thereof is as follows.
(1) Smelting of
Molten iron desulphurization, converter smelting and RH furnace refining are sequentially adopted to smelt steel according to the chemical components shown in the table 1.
[ Table 1]
(2) Continuous casting
And preparing the molten steel obtained by smelting into a continuous casting billet by adopting continuous casting equipment, wherein the thickness of the continuous casting billet is 220mm.
(3) Hot rolling
And (3) heating the continuous casting billet obtained in the continuous casting process to 1110 ℃ in a heating furnace, preserving heat for 40min, discharging, and carrying out 6-pass rough rolling, 7-pass finish rolling, cooling and coiling to prepare a hot-rolled coil plate with the thickness of 2.1 mm. Wherein the finish rolling temperature is 850 ℃, the coiling temperature is 650 ℃, the difference between the thicknesses of the middle part and the edge part of the hot rolled plate is 32 μm, and the difference between the thicknesses of the two edge parts of the hot rolled plate is 6 μm.
(4) Edge cutting
And shearing the two side parts of the hot-rolled coil by using a circle shear, wherein the shearing width of one side is 25mm.
(5) Normalized acid washing
And (3) conveying the hot rolled coil subjected to edge cutting into a normalizing furnace for normalizing at the normalizing temperature of 910 ℃ for 60s, and then pickling.
(6) Cold rolling
And (4) cold rolling the steel sheet into non-oriented silicon steel with the thickness of 0.5mm in a cold rolling line through 4 passes.
Wherein, the reduction rate in the first cold rolling is 40 percent, and the rolling speed is 80-120 m/min.
(7) Annealing the finished product
And (3) annealing the finished product of the cold-hard steel coil obtained by cold rolling in a continuous annealing furnace, wherein the annealing temperature of the finished product is 1000 ℃, and the annealing time is 30s.
(8) Coating, finishing, roll-to-roll packaging
And cooling the annealed steel strip, coating an insulating layer on the surface of the finished product and finishing to obtain the non-oriented silicon steel finished product.
Comparative examples 1 to 6 and comparative exampleDetecting the Epstein square ring sample of the non-oriented silicon steel finished product obtained in the proportion of 1-10 to obtain iron loss P 1.5/50 Magnetic induction B 5000 The data of (a) are shown in Table 2.
[ Table 2]
As can be seen from table 2, the chemical composition satisfies: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of iron loss P of the non-oriented silicon steel with the thickness of 0.5mm is prepared when the iron loss P is not more than 0.0015 percent of S, not more than 0.0020 percent of N, not more than 0.03 percent of P, not more than 0.003 percent of Ti, not more than 0.003 percent of V, not more than 0.003 percent of Nb, not more than 3.80 percent of Si + Al and not more than 4.15 percent of the balance of Fe and inevitable impurities 1.5/50 Less than or equal to 2.35W/kg, magnetic induction intensity B 5000 The steel has the advantages of more than or equal to 1.66T, ultralow iron loss and excellent magnetic performance, and can not break strip during cold rolling, thereby greatly improving the rolling yield.
The beneficial effects of the present invention will be further illustrated by 2 additional examples 7-8 and 8 comparative examples 11-18, although these 2 examples are only some, but not all, of the many variations of the present invention. 2 examples and 8 comparative examples each provide a non-oriented silicon steel, and the production method thereof is as follows.
(1) Smelting
Molten iron desulfurization, converter smelting and RH furnace refining are sequentially adopted to smelt steel according to the following chemical components, and the chemical components of the molten steel comprise the following components in percentage by mass: 0.0015% of C, 3.22% of Si, 0.18% of Mn, 0.85% of Al, 0.0006% of S, 0.0011% of N, 0.021% of P, 0.0021% of Ti, 0.0015% of V, 0.0023% of Nb, and the balance of Fe and inevitable impurities.
(2) Continuous casting
And preparing the molten steel obtained by smelting into a continuous casting billet by adopting continuous casting equipment, wherein the thickness of the continuous casting billet is 220mm.
(3) Hot rolling
And (3) heating the continuous casting billet obtained in the continuous casting process to 1110 ℃ in a heating furnace, preserving heat for 40min, discharging, and carrying out 6-pass rough rolling, 7-pass finish rolling, cooling and coiling to prepare a hot-rolled coil with the thickness of 2.1 mm. Wherein the finish rolling temperature is 850 ℃, the coiling temperature is 650 ℃, the difference between the thicknesses of the middle part and the edge part of the hot rolled plate is 20-40 μm, and the difference between the thicknesses of the two edge parts of the hot rolled plate is less than 22 μm.
(4) Edge cutting
And shearing the two side parts of the hot-rolled coil by using a circle shear, wherein the shearing width of one side is 25mm.
(5) Normalized acid washing
And (3) conveying the trimmed hot rolled coil into a normalizing furnace for normalizing, wherein the normalizing temperature and the normalizing time are shown in a table 3, and then pickling.
(6) Cold rolling
The non-oriented silicon steel with the thickness of 0.5mm is obtained by cold rolling the steel in a cold rolling line for 4 times, and the strip breakage condition is shown in table 3.
Wherein, the reduction and the rolling rate in the first cold rolling are shown in Table 3.
(7) Annealing the finished product
And (3) annealing the finished product of the cold-rolled hard steel coil in a continuous annealing furnace, wherein the annealing temperature of the finished product is 1000 ℃, and the annealing time is 30s.
(8) Coating, finishing, roll-to-roll packaging
And cooling the annealed steel strip, coating an insulating layer on the surface of the finished product and finishing to obtain the finished product of the non-oriented silicon steel.
The Epstein ring samples of the finished non-oriented silicon steel products obtained in examples 7 to 8 and comparative examples 11 to 18 were examined to obtain an iron loss P 1.5/50 Magnetic induction B 5000 The data of (a) are shown in Table 3.
[ Table 3]
As can be seen from Table 3, based on the chemical composition design of the non-oriented silicon steel, the edge cutting treatment is performed on the hot-rolled coil before normalization, the process parameters in the normalization process are controlled, so that the average grain size of the steel strip after normalization can be controlled to be 139-150 μm, the cold rolling strip breakage can be prevented by further combining the control of the process parameters of the cold rolling, and the iron loss P of the non-oriented silicon steel with the thickness of 0.5mm is prepared 1.5/50 Less than or equal to 2.30W/kg, magnetic induction intensity B 5000 Not less than 1.67T, and has ultralow iron loss and higher magnetic induction intensity.
In addition, the steel sheets before cold rolling of examples 7 and 8 and comparative examples 17 and 18 were observed by a scanning electron microscope to obtain edge pictures as shown in fig. 1 to 4. As can be seen from fig. 1 to 2: micro-cracks generated by shearing the edges of the steel plate prepared by trimming before the normalizing process are passivated after high-temperature normalizing, and the sharp parts of the edges are completely passivated into circles and are difficult to expand into crack sources in the cold rolling process, so that the steel plate is difficult to break during cold rolling, and the rolling yield is greatly improved. As can be seen from fig. 3 to 4: the edge of the steel plate prepared by trimming after the normalized pickling process has more sharp shearing microcracks, and the microcracks are easy to expand into longer cracks under the action of stress in the cold rolling process and are easy to break after multi-pass rolling.
Claims (8)
1. A production method of non-oriented silicon steel with ultralow iron loss is characterized by comprising the following procedures,
smelting: molten iron desulfurization, converter smelting and RH furnace refining are sequentially adopted for smelting steel, and the finally obtained molten steel comprises the following chemical components in percentage by mass: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of S is less than or equal to 0.0015 percent, N is less than or equal to 0.0020 percent, P is less than or equal to 0.03 percent, ti is less than or equal to 0.003 percent, V is less than or equal to 0.003 percent, nb is less than or equal to 0.003 percent, and simultaneously, the Si + Al is more than or equal to 3.80 percent and less than or equal to 4.15 percent, and the balance of Fe and inevitable impurities;
continuous casting: continuously casting molten steel obtained by smelting into a continuous casting billet;
hot rolling: heating the continuous casting billet, and then performing multi-pass rolling to obtain a hot-rolled coil plate with the thickness of 1.9-2.3 mm, wherein the thickness difference between the middle part and the edge part of the hot-rolled coil plate is 20-40 mu m, and the thickness difference between the two edge parts of the hot-rolled coil plate is less than or equal to 22 mu m;
trimming: shearing the edges of the two sides of the hot-rolled coil, wherein the shearing width of one side is more than or equal to 20mm;
normalizing and pickling: the normalizing temperature is 900-930 ℃, and the normalizing time is 30-60 s;
cold rolling: the non-oriented silicon steel with the thickness of 0.35-0.5 mm is obtained through multi-pass cold rolling, wherein the reduction rate in the first cold rolling is more than or equal to 37 percent, and the rolling speed is 70-180 m/min.
2. The method for producing the ultra-low iron loss non-oriented silicon steel according to claim 1, wherein in the smelting process, the chemical compositions of the finally obtained molten steel are as follows by mass percent: c is less than or equal to 0.003 percent, si:2.8 to 3.4%, mn:0.1 to 0.5%, al:0.6 to 1.3 percent of the total weight of the alloy, less than or equal to 0.0010 percent of S, less than or equal to 0.0015 percent of N, less than or equal to 0.03 percent of P, less than or equal to 0.003 percent of Ti, less than or equal to 0.003 percent of V, less than or equal to 0.003 percent of Nb, 3.80 percent to 4.15 percent of Si + Al, and the balance of Fe and inevitable impurities.
3. The method for producing the ultra-low core loss non-oriented silicon steel according to claim 1, wherein in the hot rolling process, the obtained continuous casting slab is heated to 1080-1130 ℃ and kept warm for 30-50 min.
4. The method for producing ultra-low core loss non-oriented silicon steel according to claim 1, wherein in the hot rolling step, the finish rolling temperature of the hot rolling is 830 to 870 ℃, and the coiling temperature is 620 to 680 ℃.
5. The method for producing ultra-low core loss non-oriented silicon steel according to claim 1, wherein the normalized steel strip has an average grain diameter of 130 to 150 μm.
6. The method for producing an ultra-low core loss non-oriented silicon steel as claimed in claim 1, further comprising: annealing the cold-rolled hard steel coil by a continuous annealing furnace to obtain a finished product, wherein the annealing temperature of the finished product is 950-1000 ℃, and the annealing time is 20-30 s; and cooling, coating and finishing the annealed steel strip to obtain a finished product of the non-oriented silicon steel.
7. Ultra-low iron loss non-oriented silicon steel, characterized in that the silicon steel is prepared by the production method as claimed in any one of claims 1 to 6.
8. The ultra-low iron loss non-oriented silicon steel as claimed in claim 7, wherein the thickness of the finished ultra-low iron loss non-oriented silicon steel product is 0.5mm, and the iron loss P is 1.5/50 Not more than 2.35W/kg, and magnetic induction intensity B 5000 ≥1.66T；
Or the thickness of the finished product of the ultra-low iron loss non-oriented silicon steel is 0.35mm, and the iron loss P of the finished product is 1.5/50 Less than or equal to 2.10W/kg, magnetic induction intensity B 5000 ≥1.65T。
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