CN114045434A - High-grade non-oriented silicon steel and production method thereof - Google Patents
High-grade non-oriented silicon steel and production method thereof Download PDFInfo
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Abstract
The invention discloses high-grade non-oriented silicon steel and a production method thereof, wherein the production method comprises smelting, continuous casting, hot rolling, acid washing, trimming, normalizing and cold rolling, and the chemical components of molten steel obtained finally by smelting are as follows in percentage by mass: less than or equal to 0.005 percent of C, more than or equal to 2.8 percent of Si, 0.5-1.2 percent of Als, 0.25-0.8 percent of Mn, less than or equal to 0.02 percent of P, less than or equal to 0.0040 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Nb, less than or equal to 0.0020 percent of V, less than or equal to 0.0020 percent of Ti, and the balance of Fe and inevitable impurities; the edge cutting process is used for cutting edges of two sides of the hot-rolled coil, and the cutting width of one side is 10-20 mm; normalizing in a cover annealing furnace, wherein the soaking temperature is T (990-1010) -100 x (30 x (Si) +20 x (Al)), the soaking time is 6h, and then cooling; and cooling the steel coil to a preset temperature T0 in a cover annealing furnace, taking out the steel coil and conveying the steel coil to a cold rolling line for cold rolling, wherein the T0 is 120-180 ℃, the rolling force during the first rolling is constant and is 11000-12000 kN. The method can avoid frequent strip breakage caused by high brittleness of the high-grade non-oriented silicon steel in the cold rolling process.
Description
Technical Field
The invention belongs to the technical field of steel smelting, relates to a production method of high-grade non-oriented silicon steel, and further relates to the high-grade non-oriented silicon steel prepared by the production method.
Background
Non-oriented silicon steel is a core material for rotors of motors and generators operating in a rotating magnetic field, and requires good magnetic properties, including lower core loss and higher magnetic induction. High-grade non-oriented silicon steel is one of important materials for manufacturing various large-scale generators. In recent years, with the continuous upgrading of the energy consumption of motors, the requirement on the magnetic performance of high-grade non-oriented silicon steel is higher and higher.
According to the technical standards and technical agreements of various countries, the iron loss P is generally determined1.5/50The non-oriented silicon steel with the weight not more than 4.00W/kg is called high-grade non-oriented silicon steel, and the high-grade non-oriented silicon steel is mainly divided into 4 types according to the thickness specification: 0.35mm thickness series, 0.50mm thickness series, special thick specification series and special thin specification series.
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 recrystallization temperature of silicon steel is increased, and the strip steel is difficult to completely recrystallize in the hot rolling process, so that a large amount of hot rolling deformation tissues are reserved. In order to improve the structure and texture of the hot-rolled steel plate and improve the magnetic property of the cold-rolled finished product, the hot-rolled steel strip needs to be subjected to normalizing treatment. After the strip steel is subjected to the normalizing treatment, the original hot rolling deformation structure is recrystallized, crystal grains become coarse, the toughness of the strip steel is sharply reduced, the brittleness of the strip steel is increased, the strip steel is easily broken in the cold rolling process, and the rolling efficiency and the yield of the cold rolling are influenced.
Disclosure of Invention
The invention aims to provide a production method of high-grade non-oriented silicon steel, which aims to solve the technical problem that in the prior art, the high-grade non-oriented silicon steel is easy to have strip breakage accidents in the cold rolling process so as to influence the cold rolling efficiency and the yield; the invention also aims to provide the high-grade non-oriented silicon steel prepared by the production method.
In order to achieve one of the above objects, an embodiment of the present invention provides a method for producing a high-grade non-oriented silicon steel, the method comprising the steps of,
smelting: molten iron desulfurization, converter smelting and RH refining are sequentially adopted for smelting steel, and the finally obtained molten steel comprises the following chemical components in percentage by mass: less than or equal to 0.005 percent of C, more than or equal to 2.8 percent of Si, 0.5-1.2 percent of Als, 0.25-0.8 percent of Mn, less than or equal to 0.02 percent of P, less than or equal to 0.0040 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Nb, less than or equal to 0.0020 percent of V, less than or equal to 0.0020 percent of Ti, and the balance of Fe and inevitable impurities;
continuous casting: continuously casting the molten steel obtained by smelting into a continuous casting blank with the thickness of 180-230 mm;
hot rolling: heating the continuous casting billet and then performing multi-pass rolling to obtain a hot-rolled coil plate with the thickness of 2-2.3 mm;
acid washing: pickling the hot-rolled coil to remove oxide skin on the surface of the hot-rolled coil;
normalizing: normalizing the trimmed steel coil in a cover type annealing furnace, wherein the normalizing soaking temperature is T (990-1010) -100 x (30 x (Si) +20 x (Al)), and the soaking time is 6h, and then cooling;
cold rolling: and cooling the steel coil to a preset temperature T0 in a cover annealing furnace, taking out and conveying the steel coil to a cold rolling line, and rolling the steel coil into non-oriented silicon steel by multiple passes, wherein the T0 is 120-180 ℃, the rolling force during the first pass of rolling is constant, and the rolling force is 11000-12000 kN.
Preferably, the production method further comprises a finish annealing: and carrying out continuous annealing treatment on the cold-rolled steel strip, wherein the annealing temperature is 960-1000 ℃, and the annealing time is 60 s.
Preferably, in the hot rolling step, the heating temperature is 1080-1150 ℃ and the heating time is 150-200 min.
Preferably, in the hot rolling step, the finishing temperature of the hot rolling is 800 to 840 ℃ and the coiling temperature is 550 to 650 ℃.
Preferably, in the normalizing step, the normalizing temperature rise rate is 2.5 ℃/min.
Preferably, in the normalizing process, the hood-type annealing furnace is heated by using a radiant tube, and 100% of hydrogen is filled in the hood-type annealing furnace for protection.
Preferably, in the normalizing process, the cooling rate of the steel coil in the hood-type annealing furnace is 1 ℃/min.
Preferably, in the cold rolling procedure, the initial rolling temperature of the steel strip is 80-120 ℃.
Preferably, in the cold rolling process, in the first rolling, the unit tension at the inlet end is 25-35N/mm2The unit tension of the outlet end is 85-95N/mm2The rolling speed is 150 to 250 m/min.
Preferably, a total of 5 passes of rolling are adopted in the cold rolling process; and rolling by adopting double-edge waves from the second pass to the fifth pass, and rolling by adopting a bending roll, wherein the bending roll force is 50-70 kN.
Preferably, in the second pass of rolling, the unit tension at the inlet end is 45-55N/mm2The unit tension of the outlet end is 95-105N/mm2The rolling speed is 350-450 m/min; in the third rolling, the unit tension at the inlet end is 85-95N/mm2The unit tension of the outlet end is 145-155N/mm2The rolling speed is 450-550 m/min; in the fourth pass of rolling, the unit tension at the inlet end is 95-105N/mm2The unit tension of the outlet end is 115-125N/mm2The rolling speed is 650-750 m/min; in the fifth rolling pass, the unit tension at the inlet end is 95-105N/mm2The unit tension of the outlet end is 115-125N/mm2The rolling speed is 750-850 m/min.
In order to achieve the above object, an embodiment of the present invention further provides a high-grade non-oriented silicon steel, which comprises the following chemical components by mass: the high-grade non-oriented silicon steel is prepared by the production method, wherein the content of C is less than or equal to 0.005%, the content of Si is greater than or equal to 2.8%, the content of Als is 0.5-1.2%, the content of Mn is 0.25-0.8%, the content of P is less than or equal to 0.02%, the content of S is less than or equal to 0.0040%, the content of N is less than or equal to 0.0020%, the content of Nb is less than or equal to 0.0020%, the content of V is less than or equal to 0.0020%, and the balance of Fe and inevitable impurities.
As a further improvement of one embodiment of the invention, the thickness of the high-grade non-oriented silicon steel finished product is 0.5 +/-0.005 mm, and the iron loss is P1.5/502.4 to 2.7W/kg, magnetic induction B5000Is 1.66-1.70T.
Compared with the prior art, the invention has the beneficial effects that:
(1) by combining the component proportion and the process design, the prepared silicon steel has lower iron loss and excellent magnetic induction performance, the application energy efficiency of the silicon steel in products such as various large-scale generators is met, the temperature of a steel strip before cold rolling is improved by optimizing production processes such as hot rolling, pickling, trimming, normalizing, cold rolling and the like, the frequent strip breakage of the silicon steel in the cold rolling process is avoided, the rolling efficiency and the production yield of the high-grade non-oriented silicon steel are greatly improved, and the production cost is reduced.
(2) On the basis of the chemical composition design, the hot rolled coil is subjected to acid pickling and edge cutting before normalization, so that the edge defects of the hot rolled coil can be removed, the edge drop area of the edge is cut off, the phenomenon that the edge of the hot rolled coil becomes brittle from toughness after normalization can be avoided, the shearing stress generated by the edge cutting is released after normalization, the edge stress concentration of a steel strip in the cold rolling process is reduced, the internal reason causing the cold rolling edge crack is eradicated, the defects such as the cold rolling edge crack and the sawtooth edge are completely eliminated, the edge quality of the hot rolled coil after edge cutting is ensured, and the edge damage and the edge crack in the cold rolling process are reduced; furthermore, a cover type annealing furnace is adopted in the normalizing process, and the normalizing temperature and normalizing time are controlled by combining the chemical components and the content of the silicon steel so as to control the grain size after normalization, so that the ferrite grain structure is refined as much as possible and the ferrite grain size is reduced on the premise of ensuring complete recrystallization, thereby improving the toughness of the steel strip and reducing the risk of strip breakage during cold rolling; furthermore, the steel coil is cooled in the cover type annealing furnace after being normalized to control the temperature of the steel coil, so that the steel coil still has a certain temperature when being conveyed to a cold rolling line, the situation that the steel coil becomes brittle during cold rolling due to low temperature of the steel coil before cold rolling and is easy to break is prevented, and equipment and processes are simplified; further, constant rolling force is adopted in the first pass of the cold rolling stage, rolling force fluctuation caused by thickness change of the steel strip during rolling is avoided, the non-uniform elongation rate caused by the thickness fluctuation of the steel strip during rolling is reduced, and the strip breakage risk during rolling is reduced.
(3) Controlling the hot rolling finishing temperature and the coiling temperature to obtain as many slender grains as possible; by designing the heating mode, the heating rate and the cooling rate of the bell-type annealing furnace and filling hydrogen into the bell-type annealing furnace, the normalizing process time can be controlled, the initial rolling temperature reaches the preset temperature when the steel strip is conveyed to a cold rolling line from the bell-type annealing furnace, the microstructure of the steel strip before cold rolling is controlled, and a refined ferrite grain structure is obtained, so that the toughness of the steel strip is improved, the strip breakage rate during cold rolling is reduced, the rolling efficiency and the yield of the cold rolling are improved, and the surface of the steel strip can be prevented from being oxidized during normalizing.
(4) The method has the advantages that the thickness of a final finished product is accurately controlled by controlling a cold rolling process, including a rolling mode, a roll bending force, a rolling force of each pass, tensile tension applied to a steel strip by an inlet end and an outlet end, rolling speed and the like, particularly by controlling the reduction amount of the second pass to the fifth pass, the strip breakage rate of the steel strip during cold rolling is further reduced, the production yield of high-grade non-oriented silicon steel is improved, the production cost is reduced, and the production efficiency is improved.
Drawings
FIG. 1 is a process flow diagram of the method of the present invention for producing high grade non-oriented silicon steel.
Detailed Description
The embodiment of the invention provides a production method of high-grade non-oriented silicon steel and the high-grade non-oriented silicon steel prepared by the production method. The following describes the production method of the high-grade non-oriented silicon steel in detail, which comprises the working procedures of smelting, continuous casting, hot rolling, acid cleaning, edge cutting, normalizing, cold rolling, finished product annealing, coating and the like which are carried out in sequence.
The hot-rolled coiled plate is subjected to acid pickling and edge cutting before normalization, so that the edge drop area of the edge can be cut off, the phenomenon that the edge of the hot-rolled coiled plate becomes brittle from toughness after normalization is avoided, the shearing stress generated by the edge cutting can be released after normalization, the stress concentration of the edge of a steel strip in the cold rolling process is reduced, the edge damage and edge cracking in the cold rolling process are reduced, and the strip breakage rate in the cold rolling process is reduced.
In the embodiment, the high-grade non-oriented silicon steel has the following chemical component design scheme, and the chemical components of the high-grade non-oriented silicon steel are as follows in percentage by mass: less than or equal to 0.005 percent of C, more than or equal to 2.8 percent of Si, 0.5 to 1.2 percent of Als, 0.25 to 0.8 percent of Mn, less than or equal to 0.02 percent of P, less than or equal to 0.0040 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Nb, less than or equal to 0.0020 percent of V, less than or equal to 0.0020 percent of Ti, and the balance of Fe and inevitable impurities.
The effect of each element in the chemical composition design scheme in the non-oriented silicon steel is explained as follows.
C: in non-oriented silicon steel, C is generally considered as a harmful element, and the increase of the C content can cause fine crystal grains, high iron loss, poor magnetic characteristics and cause magnetic aging problems of finished products, so that the lower the C content is generally controlled, the better the C content is; in the embodiment, the content of C (by mass percent) is controlled to be less than or equal to 0.005 percent, so that the austenite region can be enlarged.
Si: the silicon-based alloy steel is an effective addition element for improving the resistivity of an electromagnetic steel plate and reducing the iron loss, and can also effectively improve the strength of a steel strip, and in the embodiment, the content of Si (calculated by mass percent) is controlled to be more than or equal to 2.8 percent so as to effectively reduce the iron loss and meet the requirement of high-grade non-oriented silicon steel.
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; when the content is low, the resistivity is too low, and nitrides such as AlN are finely precipitated to deteriorate the grain growth, so that the requirement of low iron loss cannot be satisfied, and therefore, the content of Als (that is, acid-soluble aluminum) is controlled to 0.5 to 1.2% in the present invention.
Mn: mn is easy to react with S to generate MnS, the hot brittleness caused by S can be inhibited by adding a proper amount of Mn, the solid solubility of MnS in austenite is lower than that of MnS in a ferrite phase, the coarsening of MnS can be promoted, and the growth of crystal grains can be promoted; in the embodiment, the Mn is added and the Mn content (in mass percent) is controlled to be 0.25-0.8%, which is beneficial to enlarging an austenite region, reducing the austenite-ferrite transformation temperature, increasing the resistance and reducing the iron loss.
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 iron loss, but for high-grade non-oriented silicon, the cold ductility of the steel can be remarkably deteriorated by more than 0.05 percent; in the embodiment, because the contents of Si and Mn are high, the strength of the produced steel strip is high enough, and meanwhile, in order to avoid influencing the realization of deep removal of S in the RH smelting process, the content of P is controlled to be less than or equal to 0.02 percent.
S: the Mn-S alloy is a harmful element and is an important constituent element of inclusion components 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 hindered, 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 0.0040 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 inclusion components in steel, and AlN formed in a steel billet can be dissolved in a large amount in the hot rolling and heating process and then dispersed and precipitated in the hot processing process, so that the growth of crystal grains in the annealing process of a finished product can be hindered, and the magnetism of the finished product is reduced, so that the content of the AlN is controlled to be less than or equal to 0.0020 percent.
Nb, V: nb and V 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 0.0020%.
Ti: because the Al content in the high-grade non-oriented silicon steel is high, TiO in slag can be 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, fine precipitates of the Ti can hinder the growth of finished product crystal grains in the annealing process, the magnetic performance of the non-oriented silicon steel is deteriorated, the iron loss is increased, the magnetic induction intensity is reduced, and the Ti content is controlled to be less than or equal to 0.0020%.
In the aspect of chemical composition design, C and Mn are added on the basis of increasing Si and Als contents and reducing iron loss by designing the contents of C, Si, Als and Mn so as to enlarge an austenite region and avoid the increase of austenite-ferrite transformation temperature caused by the increase of Si content; in addition, the content of C, Si, Als and Mn is designed, and the control of elements such as S and P is matched, so that the probability of precipitating fine MnS in the hot rolling process is reduced, the content of N, Nb, V and Ti is controlled, the magnetic property is ensured, and low iron loss and high magnetic induction strength are realized.
Referring to fig. 1, the method for producing the high-grade non-oriented silicon steel of the present embodiment includes the following steps.
(1) Smelting
Molten iron desulfurization, converter smelting and RH 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: less than or equal to 0.005 percent of C, more than or equal to 2.8 percent of Si, 0.5 to 1.2 percent of Als0.25 to 0.8 percent of Mn, less than or equal to 0.02 percent of P, less than or equal to 0.0040 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Nb, less than or equal to 0.0020 percent of V, less than or equal to 0.0020 percent of Ti, and the balance of Fe and inevitable impurities.
(2) Continuous casting
Specifically, molten steel obtained by smelting is prepared into a continuous casting billet with the thickness of 180-230 mm by adopting continuous casting equipment, and the specific operation of the continuous casting process can be realized by adopting the existing feasible continuous casting technology, so that redundant description is omitted.
(3) Hot rolling
And (3) sequentially heating, carrying out multi-pass rough rolling, multi-pass finish rolling, cooling and coiling the continuous casting billet obtained in the continuous casting process to prepare a hot-rolled coil with the thickness of 2-2.3 mm.
The heating temperature is 1080-1150 ℃, the heating time is 150-200 min, an intermediate blank with the thickness of 40-45 mm is obtained through multi-pass rough rolling after heating, and a hot-rolled coil with the thickness of 2-2.3 mm is obtained through multi-pass finish rolling, cooling and coiling.
Wherein the finish rolling temperature of the finish rolling is 800-840 ℃, and the coiling temperature is 550-650 ℃.
Thus, on the basis of the design of the chemical components, the hot rolling process adopts low-temperature rolling and low-temperature coiling, and combines the control on the heating time of the continuous casting billet, so that the production efficiency is ensured, the high-temperature finish rolling of subsequent finish rolling is facilitated, the probability of precipitating fine MnS is reduced, the solid solution of precipitates such as MnS and the like in the steel in the heating process is prevented, the growth of tissue grains is facilitated, and the excellent magnetic performance of the subsequent obtained non-oriented silicon steel finished product is further ensured; the thickness of the intermediate blank after rough rolling is controlled in a combined manner, and the finish rolling temperature of finish rolling is controlled in a two-phase region or a high-temperature ferrite region, so that high-temperature ferrite is formed, and a deformed fiber structure is avoided.
(4) Acid pickling
The hot rolled coil is continuously pickled to remove the scale on the surface thereof.
(5) Edge cutting
And trimming two sides of the hot-rolled coiled plate by using a circle shear, wherein the shearing width of one side is 10-20 mm.
Therefore, on the basis of the chemical composition design, the edge defects of the hot-rolled coil can be removed by trimming the hot-rolled coil before normalization, the edge drop area of the edge is cut off, the phenomenon that the edge of the hot-rolled coil becomes brittle from toughness after normalization can be avoided, the shearing stress generated by trimming can be released after normalization, the edge stress concentration of a steel strip in the cold rolling process is reduced, the inherent reason causing the cold-rolled edge crack is eradicated, the defects such as the cold-rolled edge crack and the sawtooth edge are completely eliminated, the edge quality of the hot-rolled coil after trimming is ensured, and the edge damage and the edge crack in the cold rolling process are reduced.
(6) Normalizing
And (3) normalizing the trimmed steel coil in a cover annealing furnace, wherein the normalizing soaking temperature is T (990-1010) -100 x (30 x (Si) +20 x (Al)), and the soaking time is 6h, and then cooling.
Wherein the normalizing temperature rise rate is controlled to be 2.5 ℃/min.
Specifically, the hood-type annealing furnace is heated by adopting a radiant tube, and 100% of hydrogen is filled in the hood-type annealing furnace for protection.
Preferably, the steel coil is cooled in the hood-type annealing furnace at a cooling rate of 1 ℃/min.
Firstly, the normalizing process can improve the structure and product magnetism of the non-oriented silicon steel hot rolled steel plate and improve the condition of inconsistent head, middle and tail magnetic properties, particularly, the normalizing process is performed by adopting a cover type annealing furnace, the normalizing temperature and normalizing time are controlled by combining chemical components and content of silicon steel so as to control the grain size after normalizing, complete recrystallization can be ensured, the ferrite grain structure is refined, the average grain size of the steel strip after normalizing is controlled to be not more than 90 mu m, the toughness of the steel strip is improved, and the strip breakage risk during cold rolling is reduced. Secondly, by designing the heating mode, the heating rate and the cooling rate of the bell-type annealing furnace and filling hydrogen into the bell-type annealing furnace, the normalizing process time can be controlled, the temperature of the steel coil is controlled, the steel strip still has certain temperature when being conveyed to a cold rolling line from the bell-type annealing furnace, the initial rolling temperature is controlled, the microstructure of the steel strip before cold rolling is controlled, and a refined ferrite grain structure is obtained, so that the toughness of the steel strip is improved, the strip breakage rate during cold rolling is reduced, the rolling efficiency and the yield of the cold rolling are improved, and the surface of the steel strip can be prevented from being oxidized during normalizing. Moreover, the equipment and the working procedures are simplified, the time and the cost are saved, and the efficiency is improved.
(7) Cold rolling
And cooling the steel coil to a preset temperature T0 in a cover annealing furnace, taking out and conveying the steel coil to a cold rolling line, and rolling the steel coil into high-grade non-oriented silicon steel through multiple passes, wherein the T0 is 120-180 ℃, the rolling force during the first pass of rolling is constant, and the rolling force is 11000-12000 kN.
In the embodiment, the cold rolling process adopts 5 passes in total, and the steel strip is rolled from the thickness of 2.2-2.5 mm to the high-grade non-oriented silicon steel with the thickness of 0.5mm, so as to meet the size requirement of the high-grade non-oriented silicon steel.
Wherein, in the first rolling, a steel belt with the thickness of 2.2-2.5 mm is rolled, the initial rolling temperature is 80-120 ℃, the rolling force is constant and is 11000-12000 kN, and the unit tension at the inlet end is 25-35N/mm2The unit tension of the outlet end is 85-95N/mm2The rolling speed is 150 to 250 m/min. Wherein the inlet end is the uncoiling side and the outlet end is the coiling side. By adopting constant rolling force in the first pass, the rolling force is kept constant in the first pass rolling process, the thickness of the steel strip after the first pass rolling is not considered, the tensile tension of the inlet end and the outlet end is further controlled in a smaller range, the rolling speed is controlled in a lower range, the rolling force fluctuation caused by the thickness change of the steel strip during rolling is avoided, the uneven elongation rate caused by the thickness fluctuation of the steel strip during rolling is reduced, and the strip breakage risk during rolling is reduced.
And (3) rolling by adopting double-side wave from the second pass to the fifth pass, adopting bending roll to press, wherein the bending roll force is 50-70 kN, and the two ends of the bending roll are gradually bent towards the direction far away from the steel strip relative to the middle part of the bending roll, so that the rolling force applied to the two side parts of the steel strip is smaller than that applied to the middle part of the steel strip, and the difference between the rolling force applied to the two side parts of the steel strip and the rolling force applied to the middle part of the steel strip is the bending roll force. Therefore, stress can be more concentrated in the middle of the steel strip, and stress of the edge parts on two sides of the steel strip is relaxed, so that edge damage and edge cracking in the cold rolling process are reduced, and the quality of the edge part of the steel strip is ensured.
In the second pass of rolling, the unit tension at the inlet end is 45-55N/mm2The unit tension of the outlet end is 95-105N/mm2The rolling speed is 350-450 m/min, and the outlet isThe thickness of the steel strip is 1.1mm, namely the thickness of the steel strip is reduced to 1.1mm through the second pass of rolling.
In the third rolling, the unit tension at the inlet end is 85-95N/mm2The unit tension of the outlet end is 145-155N/mm2The rolling speed is 450-550 m/min, the pass reduction is 27.3%, the thickness of the steel strip at an outlet is 0.8mm, namely the thickness of the steel strip is rolled to be 0.8mm through the third pass rolling.
In the fourth pass of rolling, the unit tension at the inlet end is 95-105N/mm2The unit tension of the outlet end is 115-125N/mm2The rolling speed is 650-750 m/min, the pass reduction is 25%, the thickness of the steel strip at the outlet is 0.6mm, namely the thickness of the steel strip is rolled to be 0.6mm through the fourth pass rolling.
In the fifth rolling pass, the unit tension at the inlet end is 95-105N/mm2The unit tension of the outlet end is 115-125N/mm2The rolling speed is 750-850 m/min, the pass reduction is 16.7%, the thickness of the steel strip at the outlet is 0.5mm, namely the thickness of the steel strip is rolled to be 0.5mm through the fifth pass rolling.
Further controlling the process parameters from the second pass to the fifth pass, including the rolling force of each pass, the tensile tension applied to the steel strip by the inlet end and the outlet end, the rolling speed and the like, and controlling the tensile tension and the rolling speed of the inlet end and the outlet end within a lower range, so that the non-uniform elongation rate caused by the thickness fluctuation of the steel strip during rolling is reduced, and the risk of strip breakage during rolling is reduced; in addition, the rolling reduction is controlled from the second pass to the fifth pass, so that the thickness of a final finished product is accurately controlled, the strip breakage rate of the steel strip in cold rolling is further reduced, the production yield of high-grade non-oriented silicon steel is improved, the production cost is reduced, and the production efficiency is improved.
(8) Annealing the finished product
And carrying out continuous annealing treatment on the cold-rolled steel strip, wherein the annealing temperature is 960-1000 ℃, and the annealing time is 60 s.
(9) Coating layer
The upper and lower surfaces of the steel strip are uniformly coated with insulating layers to improve the insulating property of the steel strip.
The high-grade non-oriented silicon steel provided by the embodiment of the invention is prepared by the production method, the thickness of the high-grade non-oriented silicon steel is 0.50 +/-0.005 mm, and the high-grade non-oriented silicon steel comprises the following chemical components in percentage by mass: less than or equal to 0.005 percent of C, more than or equal to 2.8 percent of Si, 0.5 to 1.2 percent of Als, 0.25 to 0.8 percent of Mn, less than or equal to 0.02 percent of P, less than or equal to 0.0040 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Nb, less than or equal to 0.0020 percent of V, less than or equal to 0.0020 percent of Ti, and the balance of Fe and inevitable impurities.
When the production method is adopted to prepare the high-grade non-oriented silicon steel, the rolling strip breakage rate is less than or equal to 1 percent, and the detection shows that the iron loss P of the high-grade non-oriented silicon steel is1.5/502.4 to 2.7W/kg, magnetic induction B5000The magnetic induction performance is 1.66-1.70T, the magnetic induction performance is excellent, and the requirements of application energy efficiency of the magnetic induction system in products such as motors can be met.
Compared with the prior art, the invention has the beneficial effects that:
(1) by combining the component proportion and the process design, the prepared silicon steel has lower iron loss and excellent magnetic induction performance, the application energy efficiency of the silicon steel in products such as various large-scale generators is met, the temperature of a steel strip before cold rolling is improved by optimizing production processes such as hot rolling, pickling, trimming, normalizing, cold rolling and the like, the frequent strip breakage of the silicon steel in the cold rolling process is avoided, the rolling efficiency and the production yield of the high-grade non-oriented silicon steel are greatly improved, and the production cost is reduced.
(2) On the basis of the chemical composition design, the hot rolled coil is subjected to acid pickling and edge cutting before normalization, so that the edge defects of the hot rolled coil can be removed, the edge drop area of the edge is cut off, the phenomenon that the edge of the hot rolled coil becomes brittle from toughness after normalization can be avoided, the shearing stress generated by the edge cutting is released after normalization, the edge stress concentration of a steel strip in the cold rolling process is reduced, the internal reason causing the cold rolling edge crack is eradicated, the defects such as the cold rolling edge crack and the sawtooth edge are completely eliminated, the edge quality of the hot rolled coil after edge cutting is ensured, and the edge damage and the edge crack in the cold rolling process are reduced; furthermore, a cover type annealing furnace is adopted in the normalizing process, and the normalizing temperature and normalizing time are controlled by combining the chemical components and the content of the silicon steel so as to control the grain size after normalization, so that the ferrite grain structure is refined as much as possible and the ferrite grain size is reduced on the premise of ensuring complete recrystallization, thereby improving the toughness of the steel strip and reducing the risk of strip breakage during cold rolling; furthermore, the steel coil is cooled in the cover type annealing furnace after being normalized to control the temperature of the steel coil, so that the steel coil still has a certain temperature when being conveyed to a cold rolling line, the situation that the steel coil becomes brittle during cold rolling due to low temperature of the steel coil before cold rolling and is easy to break is prevented, and equipment and processes are simplified; further, constant rolling force is adopted in the first pass of the cold rolling stage, rolling force fluctuation caused by thickness change of the steel strip during rolling is avoided, the non-uniform elongation rate caused by the thickness fluctuation of the steel strip during rolling is reduced, and the strip breakage risk during rolling is reduced.
(3) Controlling the hot rolling finishing temperature and the coiling temperature to obtain as many slender grains as possible; by designing the heating mode, the heating rate and the cooling rate of the bell-type annealing furnace and filling hydrogen into the bell-type annealing furnace, the normalizing process time can be controlled, the initial rolling temperature reaches the preset temperature when the steel strip is conveyed to a cold rolling line from the bell-type annealing furnace, the microstructure of the steel strip before cold rolling is controlled, and a refined ferrite grain structure is obtained, so that the toughness of the steel strip is improved, the strip breakage rate during cold rolling is reduced, the rolling efficiency and the yield of the cold rolling are improved, and the surface of the steel strip can be prevented from being oxidized during normalizing.
(4) The method has the advantages that the thickness of a final finished product is accurately controlled by controlling a cold rolling process, including a rolling mode, a roll bending force, a rolling force of each pass, tensile tension applied to a steel strip by an inlet end and an outlet end, rolling speed and the like, particularly by controlling the reduction amount of the second pass to the fifth pass, the strip breakage rate of the steel strip during cold rolling is further reduced, the production yield of high-grade non-oriented silicon steel is improved, the production cost is reduced, and the production efficiency 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 3 examples and 2 comparative examples, of course, these 3 examples are only a part, but not all, of the many variations of the invention. 3 examples and 2 comparative examples respectively provide a high-grade non-oriented silicon steel, and the production method thereof is as follows.
(1) Smelting
Molten iron desulphurization, converter smelting and RH refining are sequentially adopted to smelt steel according to the chemical components shown in the 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 220 mm.
[ Table 1]
| Chemical composition in wt% | Example 1 | Example 2 | Example 3 | Comparative example 1 | Comparative example 2 |
| C | 0.002 | 0.002 | 0.002 | 0.002 | 0.002 |
| Si | 2.83 | 2.93 | 3.15 | 3.0 | 3.0 |
| Als | 0.6 | 0.95 | 1.15 | 0.8 | 0.5 |
| Mn | 0.75 | 0.45 | 0.3 | 0.25 | 0.45 |
| P | 0.018 | 0.015 | 0.013 | 0.015 | 0.015 |
| S | 0.0015 | 0.0018 | 0.0008 | 0.0020 | 0.0020 |
| N | 0.0012 | 0.0018 | 0.0013 | 0.0014 | 0.0014 |
| Nb | 0.0018 | 0.0010 | 0.0008 | 0.0013 | 0.0013 |
| V | 0.0010 | 0.0009 | 0.0012 | 0.0010 | 0.0010 |
| Ti | 0.0008 | 0.0009 | 0.0017 | 0.0009 | 0.0009 |
| Fe and inevitable impurity elements | Bal | Bal | Bal | Bal | Bal |
(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. The heating temperature, heating time, intermediate billet thickness, finish rolling temperature, and coiling temperature of examples 1 to 3 and comparative examples 1 to 2 are shown in table 2.
[ Table 2]
| Heating temperature/. degree.C | Heating time/min | Thickness of intermediate blank/mm | Final Rolling temperature/. degree.C | Coiling temperature/. degree.C | |
| Example 1 | 1138 | 150 | 45 | 840 | 650 |
| Example 2 | 1123 | 180 | 43 | 820 | 600 |
| Example 3 | 1090 | 200 | 40 | 800 | 550 |
| Comparative example 1 | 1080 | 200 | 42 | 800 | 550 |
| Comparative example 2 | 1150 | 150 | 45 | 840 | 650 |
(4) Acid pickling
Examples 1 to 3: the hot rolled coil is continuously pickled to remove the scale on the surface thereof.
Comparative examples 1 to 2: the pickling process is completed after the normalizing process, and is detailed in step 6.
(5) Edge cutting
Examples 1 to 3: and trimming two sides of the hot-rolled coiled plate by using a circle shear, wherein the shearing width of one side is 10-20 mm.
Comparative examples 1 to 2: the edge cutting process is completed after the normalizing process, and is detailed in step 6, and the shearing width of one side is 10-20 mm.
(6) Normalizing
Examples 1 to 3: normalizing the trimmed steel coil in a hood-type annealing furnace, heating the steel coil by adopting a radiant tube in the hood-type annealing furnace, and filling 100% of hydrogen in the hood-type annealing furnace for protection, wherein the normalizing temperature rise rate is 2.5 ℃/min, the normalizing soaking temperature is T (990-1010) -100 x (30 x (Si) +20 x (Al)), the soaking time is 6h, and then cooling is carried out, wherein the cooling rate is 1 ℃/min.
Comparative examples 1 to 2: heating the trimmed steel coil in a normalizing annealing furnace by open fire at a heating rate of 10 ℃/min, and electrically heating and preserving heat in a soaking section; the soaking temperature of comparative example 1 was 880 ℃ and the soaking time was 80 s; the soaking temperature of comparative example 2 was 870 ℃ and the soaking time was 80 seconds; then slowly cooling and then quickly cooling to room temperature, wherein the cooling speed of a slow cooling section is 5 ℃/s, the cooling speed of a slow cooling section is 750 ℃, the cooling speed of a quick cooling section is 20 ℃/s, and the temperature of the strip steel is below 50 ℃ after the strip steel is taken out of the furnace through the quick cooling section. And (4) performing shot blasting and pickling after discharging, and performing edge cutting treatment by using a disc shear.
(7) Cold rolling
Examples 1 to 3: the steel coil is sent to a six-roller single frame set for cold rolling when being cooled to a preset temperature T0 in a cover type annealing furnace, wherein the thickness of the steel strip at a cold rolling inlet is 2.3 mm;
comparative examples 1 to 2: and conveying the normalized steel coil to a six-roller single-rack set for cold rolling after shot blasting, pickling and trimming, wherein the thickness of the steel strip at a cold rolling inlet is 2.3 mm.
And (3) carrying out cold rolling for 5 passes, wherein the second pass rolling to the fifth pass rolling adopt double-side wave rolling, and the roll bending force is 50-70 kN. The rolling force, the unit tension at the inlet end, the unit tension at the outlet end, the rolling speed, the rolling reduction, and the thickness of the steel strip at the outlet end for 5 passes are shown in table 3.
[ Table 3]
700 rolls are continuously produced by adopting the method, the belt breakage rate of the examples 1-3 is not more than 1%, and the belt breakage rate of the comparative examples 1-2 is as high as 40%.
(8) Annealing the finished product
And carrying out continuous annealing treatment on the cold-rolled steel strip, wherein the annealing temperature is 960-1000 ℃, and the annealing time is 60 s.
(9) Coating layer
The upper and lower surfaces of the steel strip are uniformly coated with insulating layers to improve the insulating property of the steel strip.
The high-grade non-oriented silicon steel finished products obtained in the annealed examples 1-3 and comparative examples 1-2 are detected to obtain the iron loss P1.5/50And magnetic induction B5000The data of (a) are shown in Table 4.
[ Table 4]
| P1.5/50(W/kg) | B5000(T) | |
| Example 1 | 2.67 | 1.692 |
| Example 2 | 2.51 | 1.681 |
| Example 3 | 2.43 | 1.677 |
| Comparative example 1 | 2.78 | 1.661 |
| Comparative example 2 | 2.83 | 1.65 |
In combination with the whole production process, compared with the comparative examples 1 to 2, the strip breakage rate in cold rolling is greatly reduced and the rolling yield is improved in the examples 1 to 3.
In summary, it can be seen from the above examples 1 to 3 that the high-grade non-oriented silicon steel produced by the embodiment of the invention not only greatly reduces the rolling strip breakage rate and saves the cost, but also has excellent magnetic performance and reduces the iron loss.
Claims (13)
1. A production method of high-grade non-oriented silicon steel is characterized by comprising the following steps of,
smelting: molten iron desulfurization, converter smelting and RH refining are sequentially adopted for smelting steel, and the finally obtained molten steel comprises the following chemical components in percentage by mass: less than or equal to 0.005 percent of C, more than or equal to 2.8 percent of Si, 0.5-1.2 percent of Als, 0.25-0.8 percent of Mn, less than or equal to 0.02 percent of P, less than or equal to 0.0040 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Nb, less than or equal to 0.0020 percent of V, less than or equal to 0.0020 percent of Ti, and the balance of Fe and inevitable impurities;
continuous casting: continuously casting the molten steel obtained by smelting into a continuous casting blank with the thickness of 180-230 mm;
hot rolling: heating the continuous casting billet and then performing multi-pass rolling to obtain a hot-rolled coil plate with the thickness of 2-2.3 mm;
acid washing: pickling the hot-rolled coil to remove oxide skin on the surface of the hot-rolled coil;
trimming: trimming two sides of the hot-rolled coil, wherein the shearing width of one side is 10-20 mm;
normalizing: normalizing the trimmed steel coil in a cover type annealing furnace, wherein the normalizing soaking temperature is T (990-1010) -100 x (30 x (Si) +20 x (Al)), and the soaking time is 6h, and then cooling;
cold rolling: and cooling the steel coil to a preset temperature T0 in a cover annealing furnace, taking out and conveying the steel coil to a cold rolling line, and rolling the steel coil into non-oriented silicon steel by multiple passes, wherein the T0 is 120-180 ℃, the rolling force during the first pass of rolling is constant, and the rolling force is 11000-12000 kN.
2. The method of producing a high-grade non-oriented silicon steel according to claim 1, further comprising,
annealing of a finished product: and carrying out continuous annealing treatment on the cold-rolled steel strip, wherein the annealing temperature is 960-1000 ℃, and the annealing time is 60 s.
3. The method for producing high-grade non-oriented silicon steel according to claim 1, wherein the heating temperature in the hot rolling step is 1080-1150 ℃ and the heating time is 150-200 min.
4. The method for producing high-grade non-oriented silicon steel according to claim 1, wherein the hot rolling step is performed at a finishing temperature of 800 to 840 ℃ and a coiling temperature of 550 to 650 ℃.
5. The method for producing a high-grade non-oriented silicon steel according to claim 1, wherein in the normalizing step, the normalizing temperature rise rate is 2.5 ℃/min.
6. The method for producing high grade non-oriented silicon steel according to claim 1, wherein the normalizing process is performed by heating the hood-type annealing furnace with a radiant tube and filling the hood-type annealing furnace with 100% hydrogen for protection.
7. The method of claim 1, wherein the coil is cooled in the hood-type annealing furnace at a cooling rate of 1 ℃/min in the normalizing process.
8. The method for producing high-grade non-oriented silicon steel according to claim 1, wherein the cold rolling process is performed at a start rolling temperature of the steel strip of 80-120 ℃.
9. The method for producing high-grade non-oriented silicon steel according to claim 1, wherein in the cold rolling step, the unit tension at the inlet end in the first rolling is 25-35N/mm2The unit tension of the outlet end is 85-95N/mm2The rolling speed is 150 to 250 m/min.
10. The method for producing a high-grade non-oriented silicon steel according to claim 1, wherein the cold rolling step comprises a total of 5 passes; and rolling by adopting double-edge waves from the second pass to the fifth pass, and rolling by adopting a bending roll, wherein the bending roll force is 50-70 kN.
11. The method for producing high-grade non-oriented silicon steel according to claim 10, wherein the unit tension at the inlet end in the second rolling pass is 45-55N/mm2The unit tension of the outlet end is 95-105N/mm2The rolling speed is 350-450 m/min; in the third rolling, the unit tension at the inlet end is 85-95N/mm2The unit tension of the outlet end is 145-155N/mm2The rolling speed is 450-550 m/min; in the fourth pass of rolling, the unit tension at the inlet end is 95-105N/mm2The unit tension of the outlet end is 115-125N/mm2The rolling speed is 650-750 m/min; in the fifth rolling pass, the unit tension at the inlet end is 95-105N/mm2The unit tension of the outlet end is 115-125N/mm2The rolling speed is 750-850 m/min.
12. The high-grade non-oriented silicon steel is characterized by being prepared by the production method of any one of claims 1 to 11, and comprising the following chemical components in percentage by mass: the high-grade non-oriented silicon steel is prepared by the production method, wherein the content of C is less than or equal to 0.005%, the content of Si is greater than or equal to 2.8%, the content of Als is 0.5-1.2%, the content of Mn is 0.25-0.8%, the content of P is less than or equal to 0.02%, the content of S is less than or equal to 0.0040%, the content of N is less than or equal to 0.0020%, the content of Nb is less than or equal to 0.0020%, the content of V is less than or equal to 0.0020%, and the balance of Fe and inevitable impurities.
13. The high-grade non-oriented silicon steel of claim 12, wherein the thickness of the obtained high-grade non-oriented silicon steel product is 0.5 +/-0.005 mm, and the iron loss P is1.5/502.4 to 2.7W/kg, magnetic induction B5000Is 1.66-1.70T.
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| CN115198198B (en) * | 2022-09-13 | 2022-12-23 | 张家港扬子江冷轧板有限公司 | Non-oriented silicon steel for high-speed motor and preparation method thereof |
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| CN116689486B (en) * | 2023-08-07 | 2023-10-31 | 江苏省沙钢钢铁研究院有限公司 | Non-oriented silicon steel sheet and preparation method thereof |
| CN117127110A (en) * | 2023-10-27 | 2023-11-28 | 江苏省沙钢钢铁研究院有限公司 | High-grade non-oriented silicon steel with excellent surface and preparation method thereof |
| CN117127110B (en) * | 2023-10-27 | 2024-02-02 | 江苏省沙钢钢铁研究院有限公司 | High-grade non-oriented silicon steel with excellent surface and preparation method thereof |
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