CN110735088A - Non-oriented silicon steel produced by thin slabs and manufacturing method thereof - Google Patents
Non-oriented silicon steel produced by thin slabs and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses kinds of non-oriented silicon steel produced by sheet billets and a manufacturing method thereof, belonging to the technical field of non-oriented silicon steel production, wherein the chemical components of the non-oriented silicon steel comprise, by weight, not more than 0.005% of C, not more than 1.50% of Si, not less than 0.40% and not more than 0.70% of Mn, not less than 0.050% and not more than 0.55% of Als, not less than 0.0010% and not more than 0.0030% of S, not less than 0.0010% and not more than 0.0030% of N, not more than 0.0015% of Ti, and the balance Fe and inevitable impurities.
Description
Technical Field
The invention relates to the technical field of non-oriented silicon steel production, in particular to non-oriented silicon steel produced by thin slabs and a manufacturing method thereof.
Background
The main magnetic indexes of the non-oriented silicon steel are iron loss and magnetic induction intensity, and the magnetic performance of the non-oriented silicon steel is not only directly related to the loss of electric energy, but also determines the performance, volume, weight and cost of the products such as the motor, the transformer and the like, so that the magnetic performance of the non-oriented silicon steel needs to be improved by steps to meet the use requirements of miniaturization and low energy consumption of the products such as the motor, the transformer and the like.
At present, compared with the traditional silicon steel production process, the process flow of producing the non-oriented silicon steel product by the continuous casting and rolling of the thin slab comprises the steps of steel making, continuous casting and rolling, normalized pickling, cold rolling, annealing and insulating layer coating, has the advantages of short process, energy conservation, consumption reduction, partially outstanding electromagnetic performance, low production cost and the like, and is popular with metallurgical enterprises.
According to the retrieval, the application number of Chinese patent is 201410678222.9, the application date is 24/11/2014, high-magnetic-induction non-oriented silicon steel without normalization and a production method of a thin slab are invented, the non-oriented silicon steel in the application comprises, by mass, not more than 0.0030% of C, 0.1-1.0% of Si, 0.1-0.5% of Mn, not more than 0.0050% of S, 0.01-0.15% of P, not more than 0.030% of Al, not more than 0.0050% of N and 0.01-0.15% of Sn + Sb, the production steps of the silicon steel are that a steel coil is smelted and continuously cast into a slab, the steel coil is heated, coiled after conventional rolling, after conventional acid washing, continuous annealing and conventional insulating coating are carried out, the application has the preferable design of components and processes, namely, the heating temperature of the steel coil is reduced through the composite addition of Sn and Sb, the preferable selection of the coiling temperature of the steel coil is carried out, the cooling speed is strictly controlled within 20 h, the final oriented silicon steel coil is not more than 635 ℃/5, and the final oriented iron loss is not reduced (the final product is obtained by the application).
For another example, CN112962A discloses non-oriented electrical steel sheets and cores for motors or transformers with low iron loss after stress relief annealing, in which rare earth REM is added to reduce Zr and Ti, thereby coarsening and detoxifying very fine precipitates which inhibit the growth of crystal grains during stress relief annealing at low temperature for a short time, and further obtaining non-oriented silicon steel with excellent iron loss after stress relief annealing.
Disclosure of Invention
1. Problems to be solved
The invention aims to overcome the defect that the iron loss reduction effect of the obtained silicon steel product is relatively poor when the existing thin slab continuous casting and rolling is adopted to produce the non-oriented silicon steel, and provides thin slab produced non-oriented silicon steel and a manufacturing method thereof.
2. Technical scheme
In order to solve the problems, the technical scheme adopted by the invention is as follows:
the non-oriented silicon steel produced by kinds of sheet billets comprises the following chemical components, by weight, equal to or less than 0.005% of C, equal to or less than 1.50% of Si, equal to or less than 0.70% of Mn, equal to or less than 0.050% of Als, equal to or less than 0.55% of Als, equal to or less than 0.0010% of S, equal to or less than 0.0030% of S, equal to or less than 0.0010% of N, equal to or less than 0.0030% of Ti and equal to or less than 0.0015% of Fe and inevitable impurities.
Further , the contents of C, S, N and other impurities are preferably controlled to be 0.0025% or less C, 0.0010% or more S or less 0.0025% or 0.0010% or more N or less 0.0025% or less, and less than 0.006% or less other impurities, respectively.
And , reducing the iron loss P1.5/50 of the finished product of the non-oriented silicon steel to below 5.0W/kg and the magnetic permeability mu 1.0 of the product to above 6000Gs/Oe, and after stress relief annealing, reducing the iron loss P1.5/50 of the product to below 3.5W/kg and improving the magnetic permeability mu 1.0 of the product to above 10000 Gs/Oe.
The invention relates to a manufacturing method of non-oriented silicon steel produced by sheet billets, which comprises the following steps:
, smelting and continuously casting;
step two: heating;
step three: hot continuous rolling;
step four: coiling;
step five: acid washing and cold rolling;
step six: annealing the finished product;
step seven: performing withdrawal and straightening treatment;
step eight: coating an insulating layer;
step nine: and (5) stress relief annealing.
And , performing molten iron pretreatment, converter smelting and vacuum treatment on the raw material steel in the step , and then continuously casting the raw material steel into a casting blank with the thickness of 70-90 mm.
And , in the second step, the charging temperature of the casting blank is 350-850 ℃, the heating temperature of the casting blank is 950-1100 ℃, the heating time is 0.3-1 h, in the third step, the reduction rate of the pass is 55-60%, the reduction rate of the second pass is more than 55%, the final rolling temperature is 750-850 ℃, and the thickness after hot rolling is 2.0-3.0 mm.
And , preferably heating for 0.5h in the step two, coiling at 700-850 ℃ in the step four, cold-rolled thickness at 0.35-0.65 mm in the step five, annealing at 750-890 ℃ for 40-50 s in the step six, and adopting nitrogen-hydrogen mixed gas as protective atmosphere.
And , controlling the elongation of the plate to be 3-5% when the tension leveling treatment is carried out in the seventh step.
And , when the insulating layer is coated in the step eight and then drying is carried out, the drying temperature is less than 500 ℃, and the drying time is 10-20 s.
And , when the stress relief annealing treatment is carried out in the ninth step, the annealing temperature is 700-800 ℃, the annealing time is 1.5-2.5 hours, and nitrogen is used as a protective atmosphere.
3. Advantageous effects
Compared with the prior art, the invention has the beneficial effects that:
(1) the invention relates to non-oriented silicon steel produced by kinds of thin slabs, which adopts a production flow of continuous casting and rolling of the thin slabs and optimizes the content and types of components after smelting, so that kinds of non-oriented silicon steel with low iron loss and high magnetic polarization strength, wherein the content of Si is less than 1.5 percent and the content of Al is 0.05-0.5 percent can be obtained without adding precious metals.
(2) According to the non-oriented silicon steel produced by thin slabs, the content proportion of Mn in the components is optimally designed, and the related process parameters are adjusted, so that the recrystallization of a casting blank can be promoted by steps, a good hot rolling structure is obtained, the corrugation defect is eliminated, and the electromagnetic performance of the obtained non-oriented silicon steel is ensured.
(3) In the method for manufacturing the non-oriented silicon steel produced by thin slabs, steps of pulling and straightening treatment are carried out on the non-oriented silicon steel after finished product annealing in the aspect of , and finally stress relief annealing is carried out, so that the iron loss value of the non-oriented silicon steel can be reduced in the step of , the reduction ratio of the iron loss value is high, the magnetic polarization strength of the obtained non-oriented silicon steel can be improved in the step of , in the aspect of , the casting blank size and the processing technology (heating time and the like) of the non-oriented silicon steel are optimized, so that the non-oriented silicon steel produced by adopting the thin slab production process can be favorably used for playing good annealing performance requirements in the step of , and therefore the non-oriented silicon steel produced by adopting the thin.
(4) According to the manufacturing method of the non-oriented silicon steel produced by thin slabs, the components, the proportion and various process parameters of the manufacturing process of the non-oriented silicon steel are optimally designed, so that the magnetic performance and the mechanical performance of the obtained non-oriented silicon steel can be ensured in step , and the manufacturing process is simple and has low cost.
Drawings
FIG. 1 is a cross-sectional metallographic view of the annealed product of non-oriented silicon steel obtained in example 1;
FIG. 2 is a cross-sectional metallographic view of the non-oriented silicon steel product obtained in example 1 after stress relief annealing;
FIG. 3 shows the chemical composition (in weight percent) of the non-oriented silicon steel product of each example;
figure 4 shows the results of performance tests on the non-oriented silicon steel products of the examples.
Detailed Description
The invention relates to a manufacturing method of non-oriented silicon steel produced by thin slabs, which comprises the following steps:
, pretreating the raw material steel with molten iron to ensure that the content of target S is less than or equal to 0.0020% after the raw material steel is pretreated with the molten iron, then carrying out converter steelmaking to require that the oxygen content of tapping is less than or equal to 800ppm, then carrying out vacuum treatment for desulfurization, decarburization and deoxidation to ensure that the steel reaches the required component requirement, and then continuously casting the steel into a casting blank of 70-90 mm, wherein the chemical components (weight percentage) of the smelted raw material steel are less than or equal to 0.005% of C, less than or equal to 1.50% of Si, less than or equal to 0.70% of Mn, less than or equal to 0.40% of Mn, less than or equal to 0.55% of Als, less than or equal to 0.0010% of S, less than or equal to 0.0030% of N, less than or equal to 0.0015% of.
It should be noted that, since C is a main element for generating magnetic aging, it is better to control at a lower level and has a high C content, and it is necessary to perform humidification decarburization during the subsequent annealing treatment, otherwise, an internal oxidation layer is easily generated under the high temperature chamber atmosphere, which hinders the grain growth during the stress relief annealing process, thereby deteriorating the stress relief annealing performance. Therefore, C.ltoreq.0.0025% is preferred in the range of C.ltoreq.0.005%. Si is an element for increasing the resistance, is the most important alloy element of electrical steel, needs to be properly increased in order to obtain low iron loss of non-oriented silicon steel products, but the magnetic polarization strength J5000 is reduced due to the excessively high Si content, so the upper limit of the Si content is controlled to be 1.5 percent. The aluminum has similar action with silicon, and can effectively improve rho value, reduce gamma region and promote grain growth, thereby effectively reducing the iron loss of the non-oriented silicon steel.
Since Ti in the silicon steel component forms fine Ti (CN) with C, N, and S forms fine Cu with CuxTherefore, the content of S, N in the present invention is preferably controlled to be less than 0.0025%, the content of Ti is controlled to be less than 0.0015%, other impurity elements such as V, Nb should be controlled to be low, and requires that the total content be controlled to be less than 0.006%.
Step two: the charging temperature of the casting blank is controlled below 350-850 ℃, and the casting blank can pass through
The columnar crystals are crushed through phase change, but the temperature cannot be too low, so that the heating time of the casting blank is too long, and the requirement of high-efficiency production cannot be met; therefore, the heating temperature of the casting blank is controlled to be 950-1100 ℃, and the heating time is controlled to be 0.3-1 h, preferably 0.50 h;
and step three, in the hot continuous rolling process, the thickness of the plate after final hot rolling is 2.0-3.0 mm, the hot rolling pass reduction rate is controlled to be 55-60%, the second pass reduction rate is controlled to be more than 55%, high-temperature recrystallization of the hot rolled plate can be promoted, the cast structure is broken, the final rolling temperature is controlled to be 750-850 ℃, the deformation structure with fine recrystallized grains can be formed at the grain boundary by controlling the low final rolling temperature, meanwhile, the Mn content is optimally designed, and the setting of the hot continuous rolling reduction rate and the temperature is combined, so that steps can be carried out to promote the recrystallization of the casting blank, further, a good hot rolled structure is obtained, the corrugation defect is eliminated, and the optimization is more favorable for properly adjusting the Mn content under the process condition, and the product of the solid solubility of MnS in the gamma phase is lower than that in the α phase, so that the MnS can be promoted to coarsen, and the growth of the later grains is favorable for growing.
Step four: the high-temperature holding time of the strip steel is increased as much as possible before coiling, the coiling temperature is 30-50 ℃ higher than the recrystallization temperature, the recrystallization of the strip steel is promoted in the coiling process, the coarsening of second-phase particles can be promoted, and the normalizing effect is achieved. The coiling temperature is controlled to be 700-850 ℃, so that the deformed ferrite can be subjected to static recrystallization, and approximately isometric crystals are obtained;
step five, directly carrying out acid washing and cold rolling on the hot rolled plate with the thickness of 2.0-3.0 mm obtained after the treatment in the step five to the required thickness, wherein is 0.35-0.65 mm in the common way, and the normalization treatment is not needed, so that the production cost is favorably reduced;
step six: annealing the cold-rolled strip steel in a nitrogen-hydrogen mixed atmosphere at the temperature of 750-890 ℃, wherein the dew point is below-10 ℃, and annealing for 40-50 s to obtain a required recrystallization structure;
step seven: performing withdrawal and straightening treatment on the annealed strip steel by adopting a withdrawal and straightening machine, and controlling the leveling elongation of the plate to be 3-5%;
step eight: coating an insulating coating on the surface of the strip steel after the withdrawal and straightening treatment, and drying and curing at the temperature of below 500 ℃ for 10-20 s, so that the strip steel has excellent insulating property;
step nine: and (3) annealing the strip steel coated with the insulating layer at 700-800 ℃ for 1.5-2.5 h under the protection of nitrogen to finally obtain the stress-relief annealing performance of the silicon steel product.
The invention relates to a method for producing non-oriented silicon steel by adopting an existing thin slab production process, which is characterized in that when the magnetic performance of a non-oriented silicon steel plate material is optimized by controlling relevant process parameters in the production, the improvement effect of the magnetic performance of the non-oriented silicon steel plate material, particularly the reduction effect of iron loss is not obvious, and meanwhile, when the iron loss of the non-oriented silicon steel is reduced by adopting the existing thin slab production process, the magnetic induction of the non-oriented silicon steel is inevitably reduced, so that the requirements of simultaneously reducing the iron loss and improving the magnetic induction cannot be met.
The method for manufacturing the non-oriented silicon steel adopts a thin slab process, a hot rolled product obtained after continuous casting and rolling treatment has the characteristics of fine second phase and high product strength, and therefore the obtained non-oriented silicon steel cannot meet the requirement of good secondary annealing performance, the method is not favorable for the obtained non-oriented silicon steel, and the excellent electromagnetic performance brought by secondary annealing is obtained through proper process measures.
The invention is described in step with reference to specific embodiments.
Example 1
The chemical components of the test steel of this example are shown in fig. 3, the test steel is subjected to molten iron pretreatment, converter smelting and vacuum treatment, and then continuously cast into a 75mm casting blank, the total of impurity elements C + S + N + Ti is 65ppm, the casting blank charging temperature is controlled at 800 ℃, the hot continuous rolling is performed after heating at 1000 ℃ for 0.5h, the hot rolling pass reduction at is controlled at 56%, the second pass reduction is controlled at 58%, the finish rolling temperature is maintained at 800 ℃, the hot rolling is performed to form a 2.5mm thick hot rolled coil, the coiling temperature is 760 ℃, the coiled hot rolled plate is subjected to acid cleaning and then cold rolling to 0.50mm thickness, then annealing at 760 ℃ for 45S is performed, nitrogen and hydrogen mixed gas protection is adopted, before an insulating layer is coated, the strip steel is leveled according to the elongation of 5%, and then coated with the insulating layerAfter the insulating coating is dried and cured at 450 ℃ for 15s, the insulating coating is protected by nitrogen, and stress relief annealing is carried out at 750 ℃ for 2h to obtain a final product. The grain size of the finished product annealed product is about 35 mu m, the grain size of the product annealed after stress relief annealing is 52 mu m, and the metallographic structure is shown in figure 1 and figure 2. Comparing fig. 1 and fig. 2, it can be seen that the grain size of the product is obviously increased after stress relief annealing, and the iron loss is effectively reduced. Measuring iron loss P of annealed product and annealed stress-relief product by using Ebostan square ring sample1.5/50And μ 1.0, the specific results are shown in fig. 4.
Example 2
The weight percentage of the chemical components of the test steel of this embodiment is as shown in fig. 3, the test steel is continuously cast into a 75mm casting blank after molten iron pretreatment, converter smelting and vacuum treatment, the total content of impurity elements C + S + N + Ti is 62ppm, the temperature of the casting blank in the furnace is controlled at 750 ℃, the hot continuous rolling is performed after heating at 1050 ℃ for 0.5h, the reduction rate of the hot rolling pass is controlled at 58%, the reduction rate of the second pass is controlled at 58%, the finishing temperature is maintained at 800 ℃, the hot rolling is performed to form a hot rolling coil with the thickness of 2.5mm, the coiling temperature is 800 ℃, the hot rolling plate after the coiling treatment is acid-washed and then is cold-rolled to the thickness of 0.50mm, then 780 ℃ x 45S annealing is performed, nitrogen-hydrogen mixed gas protection is performed, before the insulating layer is coated, the strip steel is leveled according to the elongation of 4%, the insulating coating is dried and cured at 450 ℃ x 15S, nitrogen protection is performed, then 750 ℃ x 2h stress relief annealing is performed, the final product is obtained, the grain size of the finished product after the finished product is annealed, the grain size of the finished product is around 43 μm, the stress relief annealing, the product is measured by adopting1.5/50And μ 1.0, the specific results are shown in fig. 4.
Example 3
The chemical components of the test steel of this example in weight percentage are shown in fig. 3, the test steel is subjected to molten iron pretreatment, converter smelting and vacuum treatment, and then continuously cast into a 70mm casting blank, the total content of impurity elements C + S + N + Ti is 80ppm, the casting blank charging temperature is controlled at 850 ℃, the casting blank is heated at 950 ℃ for 1 hour and then is subjected to hot continuous rolling, the pass reduction rate of hot rolling at is controlled at 55%, and the pass reduction rate of second pass is controlled at 55%Hot-rolled at 60% and a finishing temperature of 750 ℃ to form a hot-rolled coil with a thickness of 2.0 mm. Coiling treatment was carried out at a coiling temperature of 700 ℃. The hot rolled plate after coiling treatment is acid-washed, then is cold-rolled to the thickness of 0.50mm, and then is annealed at 750 ℃ for 40s, because the content of C is higher, in order to ensure that the performance of the finished product does not generate magnetic aging, the annealing process is humidified to achieve the aim of decarburization, and simultaneously, nitrogen-hydrogen mixed gas is adopted for protection. Before coating an insulating layer, leveling the strip steel according to the elongation of 4%, drying and curing the coated insulating paint at 450 ℃ for 10s, adopting nitrogen protection, and then performing stress relief annealing at 700 ℃ for 2.5h to obtain a final product. The grain size of the finished product annealed product is about 36 mu m, and the grain size of the product annealed after stress relief is 55 mu m. Measuring iron loss P of annealed product and annealed stress-relief product by using Ebostan square ring sample1.5/50And μ 1.0, the specific results are shown in fig. 4.
Example 4
The weight percentage of the chemical components of the test steel of this example is shown in fig. 3, the test steel is continuously cast into a 80mm casting blank after molten iron pretreatment, converter smelting and vacuum treatment, the total content of impurity elements C + S + N + Ti is 83ppm, the furnace temperature of the casting blank is controlled at 700 ℃, the hot continuous rolling is performed after heating at 1100 ℃ for 0.5h, the hot rolling pass reduction at is controlled at 60%, the second pass reduction is controlled at 55%, the finish rolling temperature is maintained at 780 ℃, the hot rolled blank is hot rolled into a hot rolled coil with the thickness of 2.5mm, the coiling temperature is 750 ℃, the hot rolled plate after coiling is pickled and then cold rolled to the thickness of 0.35mm, then the annealing at 800 ℃ x 50S is performed, nitrogen and hydrogen mixed gas protection is performed, before coating an insulating layer, the strip steel is leveled according to the elongation of 4%, the coating insulating coating is dried and cured at 500 ℃ x 15S, nitrogen protection is performed, then the stress relief annealing at 800 ℃ x 1.5h is performed, the final product is obtained, the grain size of the finished product annealed, the product has the grain size of about 40 μm, the product has stress relief, the stress relief of the product after annealing, the stress relief of the product has the stress of1.5/50And μ 1.0, the specific results are shown in fig. 4.
Example 5
This example tests the chemical composition of the steelAccording to the weight percentage shown in figure 3, test steel is subjected to molten iron pretreatment, converter smelting and vacuum treatment and then is continuously cast into a casting blank with the thickness of 90mm, the total content of impurity elements C + S + N + Ti is 88ppm, the furnace feeding temperature of the casting blank is controlled at 350 ℃, the casting blank is heated at 1050 ℃ for 0.3h and then is subjected to hot continuous rolling, the reduction rate of the pass of the hot rolling is controlled at 58%, the reduction rate of the second pass of the hot rolling is controlled at 57%, the final rolling temperature is kept at 850 ℃, the hot rolling is hot-rolled into a hot-rolled coil with the thickness of 3.0mm, coiling is carried out, the coiling temperature is 850 ℃, the hot-rolled plate after coiling is subjected to acid cleaning and then is subjected to cold rolling to the thickness of 0.65mm, then 890 ℃ multiplied by 45S annealing is carried out, nitrogen-hydrogen mixed gas protection is adopted, before an insulating layer is coated, the strip steel is flattened according to the elongation rate of 3%, the insulating coating is dried and cured at 450 ℃ by 20S, nitrogen protection is carried out, then is subjected to 750 ℃ multiplied by 2h stress relief annealing, and finally the finished product is obtained, the finished product is annealed, the finished product with the1.5/50And μ 1.0, the specific results are shown in fig. 4.
Comparative example 1
The chemical components of the test steel of this embodiment are, by weight, as shown in fig. 3, the test steel is subjected to molten iron pretreatment, converter smelting, vacuum treatment, and then continuously cast into a 75mm casting blank, the total of impurity elements C + S + N + Ti is 86ppm, the casting blank is fed into a furnace at 800 ℃, the hot continuous rolling is performed after being heated at 1000 ℃ for 0.5 hour, the hot rolling pass reduction is controlled at 56% in th hot rolling pass, the second pass reduction is controlled at 58% in final rolling temperature, the final rolling temperature is maintained at 800 ℃, the hot rolled blank is hot rolled into a 2.5mm thick hot rolled coil, the coiling temperature is 680 ℃, the coiled hot rolled plate is pickled and then cold rolled to 0.50mm thick, then 760 ℃ x 45S annealing is performed, the C content is high to ensure that the performance of the finished product does not generate magnetic aging, the annealing process is humidified to achieve decarburization, the pulling and straightening is not performed by using nitrogen-hydrogen mixed gas protection, the insulating paint is directly coated at 450 ℃ x 15S, after drying and curing, the nitrogen protection is performed, the stress is then the finished product is removed by 750 ℃ x 2 hours, the annealing, the finished product is obtained, and the product is annealed, the product with theMethod for measuring iron loss P of annealed finished product and annealed stress relief product by using Boston square ring sample1.5/50And μ 1.0, the specific results are shown in fig. 4.
Comparative example 2
The chemical components of the test steel of the embodiment are shown in weight percentage in fig. 3, the test steel is subjected to molten iron pretreatment, converter smelting and vacuum treatment, and then is continuously cast into a 75mm casting blank, the total content of impurity elements C + S + N + Ti is 87ppm, the furnace feeding temperature of the casting blank is controlled at 750 ℃, the hot continuous rolling is carried out after being heated at 1050 ℃ for 0.5h, the hot rolling pass reduction rate of is controlled at 58%, the second pass reduction rate is controlled at 58%, the final rolling temperature is maintained at 800 ℃, a hot rolling coil with the thickness of 2.0mm is obtained through hot rolling, coiling is carried out at 670 ℃, the coiled hot rolling plate is acid-washed and then is cold-rolled to the thickness of 0.50mm, then 780 ℃ x 45S annealing is carried out, nitrogen-hydrogen mixed gas protection is adopted, before an insulating layer is coated, the pulling correction treatment is not carried out, insulating paint is directly coated, after being dried and cured at 450 ℃ x 15S, nitrogen protection is carried out, then 750 ℃ x 2h stress relief annealing is carried out, and finally the final product is obtained, the grain size of the finished product is about 43 μm, the product is subjected to stress relief annealing, the product is measured by a Bose coil1.5/50And μ 1.0, the specific results are shown in fig. 4.
Referring to fig. 4, it can be seen that the non-oriented silicon steel products obtained in examples 1 to 5 and comparative examples 1 to 2 all had iron loss reduced by steps and magnetic permeability increased by steps after stress relief annealing, however, the iron loss reduction rate of examples 1 to 5 was more than 24%, and particularly, the iron loss reduction rate was more significant than that of comparative example 2 (the iron loss reduction rate was 12.18%).
Claims (10)
- The non-oriented silicon steel produced by kinds of sheet billet is characterized by that its chemical composition includes (wt%) C less than 0.005%, Si less than 1.50%, Mn less than 0.70% and less than 0.40%, Als less than 0.55% and less than 0.050%, S less than 0.0030% and less than 0.0010%, N less than 0.0030% and Ti less than 0.0015%, and the rest is Fe and inevitable impurity.
- 2. The non-oriented silicon steel produced by kinds of thin slabs as claimed in claim 1, wherein the contents of C, S, N and other impurities are preferably controlled to be C.ltoreq.0.0025%, S.ltoreq.0.0010% or more and S.ltoreq.0.0025%, N.ltoreq.0.0010% or more and N.ltoreq.0.0025%, and other impurities are < 0.006%.
- 3. The non-oriented silicon steel produced by kinds of thin slabs according to claim 1, wherein the finished product of the non-oriented silicon steel has an iron loss P1.5/50 below 5.0W/kg and a product magnetic permeability μ 1.0 above 6000Gs/Oe, and after stress relief annealing, the iron loss P1.5/50 is reduced to below 3.5W/kg, and the product magnetic permeability μ 1.0 is increased to above 10000 Gs/Oe.
- 4, A method for manufacturing non-oriented silicon steel produced from thin slabs according to any of of claims 1 to 3, comprising the steps of:, smelting and continuously casting;step two: heating;step three: hot continuous rolling;step four: coiling;step five: acid washing and cold rolling;step six: annealing the finished product;step seven: performing withdrawal and straightening treatment;step eight: coating an insulating layer;step nine: and (5) stress relief annealing.
- 5. The method for manufacturing the non-oriented silicon steel produced by kinds of thin slabs according to claim 4, wherein the raw material steel in the step is subjected to molten iron pretreatment, converter smelting and vacuum treatment to be continuously cast into a casting blank with the thickness of 70-90 mm.
- 6. The method for manufacturing the non-oriented silicon steel produced by kinds of thin slabs according to claim 4, wherein the casting blank feeding temperature in the second step is 350-850 ℃, the casting blank heating temperature is 950-1100 ℃, the heating time is 0.3-1 h, the reduction rate of the th pass in the third step of hot continuous rolling is 55-60%, the reduction rate of the second pass is more than 55%, the final rolling temperature is 750-850 ℃, and the thickness after hot rolling is 2.0-3.0 mm.
- 7. The method for manufacturing the non-oriented silicon steel produced by kinds of thin slabs according to claim 4, wherein the heating time in the second step is preferably 0.5h, the coiling temperature in the fourth step is 700-850 ℃, the thickness after the cold rolling in the fifth step is 0.35-0.65 mm, the annealing temperature in the sixth step is 750-890 ℃, the annealing time is 40-50 s, and a nitrogen-hydrogen mixed gas is used as a protective atmosphere.
- 8. The method for manufacturing the non-oriented silicon steel produced from kinds of thin slabs according to claim 4, wherein the elongation of the slab is controlled to be 3-5% when the withdrawal and straightening treatment is performed in the seventh step.
- 9. The method for manufacturing the non-oriented silicon steel produced by kinds of thin slabs according to claim 4, wherein the drying temperature is less than 500 ℃ and the drying time is 10-20 s when the drying treatment is performed after the insulating layer is coated in the step eight.
- 10. The method for manufacturing the non-oriented silicon steel produced by kinds of thin slabs according to claim 4, wherein the annealing temperature is 700-800 ℃, the annealing time is 1.5-2.5 hours, and nitrogen is used as a protective atmosphere when the stress relief annealing treatment is performed in the ninth step.
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