CN113604743A - Method for preparing high-magnetic-induction high-strength non-oriented electrical steel by step control - Google Patents
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Abstract
A method for preparing high-magnetic-induction high-strength non-oriented electrical steel by step control comprises the following steps: (1) smelting molten steel by adopting a converter according to set components to prepare a continuous casting billet, wherein the continuous casting billet contains 0.001-0.008% of C, 1.5-4.8% of Si, 0.5-2% of Cu, 0.5-1.5% of Ni, 0.2-1% of Al, 0.2-1.5% of Mn, 0.005% of P, 0.005% of S and the balance of Fe; (2) placing the continuous casting slab in a soaking pit for heat preservation, and carrying out multi-pass hot rolling on two adjacent passes for 30-180 s; air cooling; (3) normalizing; (4) cold rolling for multiple passes; (5) annealing treatment; (6) and (5) aging treatment. The method has the advantages of low cost and simple process, and the produced non-oriented electrical steel has excellent force and magnetic properties and can well meet the use requirements of a driving/traction motor.
Description
Technical Field
The invention relates to the technical field of electrical steel manufacturing, in particular to a method for preparing high-magnetic-induction high-strength non-oriented electrical steel by step control.
Background
The high-strength non-oriented electrical steel is a key material used as a driving/traction motor of a new energy automobile and a high-speed motor car, and along with the development of the industry, the demand for the high-strength non-oriented electrical steel is increased day by day, and higher requirements on the strength and the like of the non-oriented electrical steel are also provided.
The performance of the non-oriented electrical steel directly affects the power characteristics, service performance and energy consumption level of the driving/traction motor; therefore, it is very important to develop the industry to manufacture high strength non-oriented electrical steel having excellent magnetic properties. Various methods have been disclosed for obtaining high-strength non-oriented electrical steel, and mechanical properties of non-oriented electrical steel are provided by solid-solution strengthening, precipitation strengthening, and dislocation strengthening. In the invention of patent publication No. CN 102453838A, the mechanical properties of the non-oriented electrical steel are improved by adding solid solution strengthening elements such as nickel and chromium, elements harmful to magnetic properties are controlled, and the annealing process is optimized to prepare the non-oriented electrical steel with higher magnetic induction intensity. The mechanical properties of non-oriented electrical steel are also improved by solid solution strengthening in japanese patent publication 2011-184787 and patent publication CN 102292462 a. Japanese patent laid-open Nos. 2006-161137 and 2008-050685 utilize carbonitride precipitation to strengthen the mechanical properties. Japanese patent laid-open Nos. 2007 & 186790, 2006 & 070348, 2005 & 113185 and the like introduce dislocations into the non-oriented electrical steel by means of inhibiting recrystallization or performing secondary cold rolling after complete recrystallization, and the like, so that the finished plate obtains a higher dislocation density and strengthens the mechanical properties of the non-oriented electrical steel.
However, the mechanical properties and the magnetic properties are almost inverted, so that the magnetic material is difficult to have excellent force and magnetic properties; the above patent applications all sacrifice the magnetic properties of non-oriented electrical steel to a certain extent or have complicated production process, and have adverse factors on resource saving and environmental development.
Japanese patent publications 2010-150667, 2008-261053, 2004-315956, 2004-183066 and the like also propose precipitation of a nano Cu-rich phase to improve the magnetic properties of non-oriented electrical steel. In patent publication No. CN 107130169A, a secondary cold rolling mode is adopted, and the non-oriented electrical steel reaches the balance of magnetic induction intensity, iron loss and yield strength by controlling the secondary cold rolling reduction, an annealing process and an aging process, so that the high-strength copper-containing cold-rolled non-oriented silicon steel and the manufacturing method thereof are provided, however, the two-stage cold rolling process is complicated, the process period is long, and the productivity is low. In patent publication No. CN 110373612A, rare earth is added to form rare earth oxysulfide, the oxysulfide has a high melting point, is not easy to form solid solution during high-temperature annealing, prevents crystal grains from growing, and effectively exerts the Cu precipitation strengthening capability, so that the non-oriented electrical steel has high magnetic property and high strength, but the method has strict requirements on process conditions and is not beneficial to industrial mass production. In patent publication No. CN106282781A, Wang Yuqian et al prepared high-strength non-oriented silicon steel by a twin-roll strip casting method based on nano Cu precipitation strengthening sufficiently exert the function of nano Cu precipitation strengthening, and can greatly improve the strength while hardly affecting the magnetic performance, but the twin-roll strip casting method has small hot rolling reduction, large product structure defects and difficult control of the surface quality of a hot rolled plate.
Disclosure of Invention
Aiming at the problem that the existing high-strength non-oriented electrical steel has difficultly combined force and magnetic performance, the invention provides a method for preparing the high-strength non-oriented electrical steel by step control.
The method of the invention is carried out according to the following steps:
1. smelting molten steel by adopting a converter according to set components, removing harmful gas in the steel through RH vacuum refining treatment, decarbonizing, dephosphorizing and desulfurizing, and finally carrying out continuous casting to prepare a continuous casting billet; the continuous casting billet comprises, by mass, 0.001-0.008% of C, 1.5-4.8% of Si, 0.5-2% of Cu, 0.5-1.5% of Ni, 0.2-1% of Al, 0.2-1.5% of Mn, 0.005% of P, 0.005% of S, and the balance of Fe and inevitable impurities;
2. placing the continuous casting slab in a soaking furnace, preserving heat at 850-1150 ℃, and then carrying out multi-pass hot rolling at 720-1080 ℃, wherein the interval time between two adjacent passes of hot rolling is 30-180 s; air cooling to room temperature after hot rolling to prepare a hot rolled plate;
3. keeping the temperature of the hot rolled plate at 800-1150 ℃ for 30-180 min for normalizing, wherein the normalizing is performed under the condition of a nitrogen-hydrogen mixed atmosphere, and the volume concentration of hydrogen is 20-50%; then air-cooling to room temperature to obtain a normalizing plate;
4. cold rolling the normalized plate for multiple times to prepare a cold-rolled plate;
5. carrying out annealing treatment on the cold-rolled sheet at 900-1150 ℃ for 1-15 min, wherein the annealing treatment is carried out under the condition of a nitrogen-hydrogen mixed atmosphere, and the volume concentration of hydrogen is 20-50%; then air-cooling to room temperature to prepare an annealing plate;
6. preserving the temperature of the annealing plate at 500-700 ℃ for 5-45 min for aging treatment to separate out a nano Cu-rich phase, wherein the size of the separated phase is 1-10 nm; and then air-cooling to room temperature to obtain the high-magnetic-induction high-strength non-oriented electrical steel.
In the step 1, the thickness of the continuous casting billet is 50-350 mm.
In the step 2, the heat preservation time is 30-150 min.
In the step 2, the number of hot rolling passes is 5-20, the reduction rate of each pass is 5-20%, and the total reduction rate is 68-99.6%.
In the step 2, the thickness of the hot-rolled plate is 1.5 to 16 mm.
In the step 4, the number of cold rolling passes is 6-30, the reduction rate of each pass is 5-15%, and the total reduction rate is 66.7-99.7%.
In the step 4, the thickness of the cold-rolled plate is 0.05-0.50 mm.
In the step 3, the normalization treatment is performed by a continuous annealing method.
In the step 5, the annealing treatment is performed by a continuous annealing method.
In the step 6, the aging treatment is performed in a nitrogen atmosphere by using a hood-type annealing method.
The ratio of the lambda texture component of the high-magnetic-induction high-strength non-oriented electrical steel is more than or equal to 40 percent.
The tensile strength of the high-magnetic-induction high-strength non-oriented electrical steel is 770-820 MPa, and the yield strength is 650-700 MPa.
Magnetic induction B of the above-mentioned high-magnetic-induction high-strength non-oriented electrical steel501.55 to 1.74T, and iron loss P10/400Is 11 to 27W/kg.
When the method is used for hot rolling, the lower hot rolling temperature is adopted, the interval time between two adjacent passes of hot rolling in the continuous rolling process is prolonged, a small amount of Cu-rich phase is dynamically precipitated in the hot rolling process, the Cu-rich phase and the dynamic recrystallization interact, the orientation, the grain size and the recrystallization ratio of a dynamic recrystallization crystal nucleus are regulated and controlled, and the formation of a texture crystal nucleus with favorable magnetic performance is promoted; the Cu-rich phase is ensured to be completely dissolved by normalizing treatment, the hot rolled plate is completely recrystallized and fully grown, and the average grain size of the normalized plate is ensured to be more than 70 mu m; precipitating a nano Cu-rich phase through aging treatment, controlling the time and temperature of the aging treatment, controlling the structure of the nano Cu-rich phase to be a bcc structure, and controlling the size of a precipitated phase to be 1-10 nm; the method of the invention is a feasible method for improving the mechanical property of the non-oriented electrical steel by utilizing the nano Cu-rich phase, controls the precipitation of the nano Cu-rich phase, is expected to solve the bottleneck problem of the inverted relation of the force and the magnetic property by step-by-step regulation and control of the force and the magnetic property, and provides a new solution for the development of the high-strength non-oriented electrical steel.
According to the invention, the Cu element is added into the non-oriented electrical steel as an aging treatment strengthening element, the mechanical property of the non-oriented electrical steel is strengthened by separating out the nano Cu-rich phase during aging treatment, and by utilizing the characteristic that the separation of the nano Cu-rich phase hardly affects the structure and texture of the non-oriented electrical steel, the magnetic property of the material is optimized in a secondary cold rolling manner in a step-by-step regulation manner, so that the material reaches the expected performance index, and then the nano Cu-rich phase is separated out by aging treatment to improve the mechanical property of the material, so that the problem that the mechanical property and the magnetic property of the non-oriented electrical steel cannot be simultaneously solved.
The method has the advantages of low cost and simple process, and the produced non-oriented electrical steel has excellent force and magnetic properties and can well meet the use requirements of a driving/traction motor.
Drawings
FIG. 1 is a schematic flow chart of a method for preparing high-magnetic-induction high-strength non-oriented electrical steel by stepwise regulation according to the present invention;
FIG. 2 is a microstructure Φ of a high magnetic induction high strength non-oriented electrical steel in example 1 of the present invention2Cross-sectional view of ODF at 45 °.
Detailed Description
In the embodiment of the invention, the continuous rolling mill set is adopted for carrying out multi-pass hot rolling.
The equipment adopted by the annealing in the embodiment of the invention is a continuous annealing furnace.
The equipment adopted by the aging treatment in the embodiment of the invention is a hood-type annealing furnace.
In the embodiment of the invention, the cold rolling adopts a four-roller reversible cold rolling unit.
In the embodiment of the invention, the normalizing treatment adopts a continuous annealing mode.
In the embodiment of the invention, the annealing treatment adopts a continuous annealing mode.
In the embodiment of the invention, the number of hot rolling passes is 5-20, and the reduction rate of each pass is 5-20%.
In the embodiment of the invention, the number of cold rolling passes is 6-30, the reduction rate of each pass is 5-15%,
the following are preferred embodiments of the present invention.
Example 1
The flow is shown in figure 1;
smelting molten steel by adopting a converter according to set components, removing harmful gas in the steel through RH vacuum refining treatment, decarbonizing, dephosphorizing and desulfurizing, and finally carrying out continuous casting to prepare a continuous casting billet; the components of the continuous casting billet comprise, by mass, 0.005% of C, 3.4% of Si, 1.1% of Cu, 0.8% of Ni, 0.5% of Al, 0.8% of Mn, 0.004% of P, 0.003% of S, and the balance of Fe and inevitable impurities;
the thickness of the continuous casting billet is 80 mm;
placing the continuous casting slab in a soaking furnace, preserving heat at 1000 ℃ for 90min, and then carrying out multi-pass hot rolling at the rolling temperature of 720-1080 ℃, wherein the interval time between two adjacent passes of hot rolling is 90 s; after hot rolling, air cooling to room temperature to prepare a hot rolled plate, wherein the thickness of the hot rolled plate is 3 mm; the total reduction rate is 96.25 percent;
keeping the temperature of the hot rolled plate at 1000 ℃ for 90min for normalizing treatment, and air-cooling to room temperature to obtain a normalized plate; the normalizing treatment is carried out under the condition of nitrogen-hydrogen mixed atmosphere, wherein the volume concentration of hydrogen is 20 percent;
cold rolling the normalized plate for multiple times to prepare a cold-rolled plate; the total reduction rate is 88.3 percent; the thickness of the cold-rolled plate is 0.35 mm;
keeping the temperature of the cold-rolled sheet at 1000 ℃ for 10min for annealing treatment, and cooling the cold-rolled sheet to room temperature in air to prepare an annealed sheet; the annealing treatment is carried out under the condition of a nitrogen-hydrogen mixed atmosphere, wherein the volume concentration of hydrogen is 20 percent;
preserving the temperature of the annealing plate at 550 ℃ for 20min for aging treatment to separate out a nano Cu-rich phase, wherein the size of the separated phase is 1-10 nm; then air-cooling to room temperature to obtain the high-magnetic-induction high-strength non-oriented electrical steel; the aging treatment is carried out in a hood-type annealing mode under the condition of a nitrogen atmosphere;
the ratio of the lambda texture component of the high-magnetic-induction high-strength non-oriented electrical steel is 51.7 percent; the cross section of the texture is shown in FIG. 2;
the tensile strength of the high-magnetic-induction high-strength non-oriented electrical steel is 809MPa, and the yield strength is 689 MPa;
magnetic induction intensity B of high-magnetic-induction high-intensity non-oriented electrical steel501.73T, iron loss P10/400The weight ratio was 15.2W/kg.
Example 2
The method is the same as example 1, except that:
(1) the continuous casting billet comprises, by mass, 0.006% of C, 1.52% of Si, 0.8% of Cu, 0.6% of Ni, 0.2% of Al, 1.0% of Mn, 0.003% of P and 0.002% of S; the thickness of the continuous casting billet is 150 mm;
(2) the soaking pit is insulated at 900 ℃ for 120min, and the interval time between two adjacent passes of hot rolling is 60 s; the thickness of the hot-rolled plate is 5 mm; the total hot rolling reduction is 96.7%;
(3) keeping the temperature at 1050 ℃ for 60min for normalizing; the volume concentration of hydrogen in the mixed atmosphere is 30 percent;
(4) the total cold rolling reduction rate is 90 percent; the thickness of the cold-rolled plate is 0.50 mm;
(5) keeping the temperature at 1050 ℃ for 5min for annealing treatment; the volume concentration of hydrogen in the mixed atmosphere is 30 percent;
(6) preserving the temperature of the annealing plate at 600 ℃ for 15min for aging treatment;
the ratio of the lambda texture component of the high-magnetic-induction high-strength non-oriented electrical steel is 43.6 percent;
the tensile strength of the high-magnetic-induction high-strength non-oriented electrical steel is 786MPa, and the yield strength is 663 MPa;
magnetic induction intensity B of high-magnetic-induction high-intensity non-oriented electrical steel501.67T, iron loss P10/400It was 23.2W/kg.
Example 3
The method is the same as example 1, except that:
(1) the continuous casting billet comprises 0.002% of C, 3.12% of Si, 1.32% of Cu, 1.4% of Ni, 0.3% of Al, 0.5% of Mn, 0.002% of P and 0.004% of S in percentage by mass; the thickness of the continuous casting billet is 300 mm;
(2) the soaking pit is kept at 1100 ℃ for 60min, and the interval time between two adjacent passes of hot rolling is 45 s; the thickness of the hot-rolled plate is 3.6 mm; the total hot rolling reduction is 98.8%;
(3) keeping the temperature at 900 ℃ for 120min for normalizing treatment; the volume concentration of hydrogen in the mixed atmosphere is 50 percent;
(4) the total cold rolling reduction is 73.3 percent; the thickness of the cold-rolled plate is 0.10 mm;
(5) keeping the temperature at 1030 ℃ for 15min for annealing treatment; the volume concentration of hydrogen in the mixed atmosphere is 50 percent;
(6) preserving the heat of the annealing plate at 500 ℃ for 25min for aging treatment;
the ratio of the lambda texture component of the high-magnetic-induction high-strength non-oriented electrical steel is 58.7 percent;
the tensile strength of the high-magnetic-induction high-strength non-oriented electrical steel is 789MPa, and the yield strength is 667 MPa;
magnetic induction intensity B of high-magnetic-induction high-intensity non-oriented electrical steel501.74T, core loss P10/400The weight ratio was 13.6W/kg.
Comparative example 1
The method is the same as example 1, except that:
the initial temperature when the non-oriented electrical steel continuous casting billet is subjected to hot rolling is 1100 ℃, the finish rolling temperature is 950 ℃, and the start rolling temperature and the finish rolling temperature are higher than those of the embodiment 1; the strength of the finished board prepared was similar to that of example 1, magnetic induction B501.59T, iron loss P10/40033.4W/kg, the magnetic induction is greatly reduced, and the iron loss is obviously improved.
Comparative example 2
The method is the same as example 1, except that:
the aging treatment time is 60min, the time is greatly prolonged, the structure of the nano Cu-rich phase is an fcc structure, and the size of a precipitated phase exceeds 40 nm; the prepared finished plate has the tensile strength of 613MPa, the yield strength of 507MPa and similar magnetic properties, but the strength is greatly reduced.
Claims (10)
1. A method for preparing high-magnetic-induction high-strength non-oriented electrical steel by step control is characterized by comprising the following steps:
(1) smelting molten steel by adopting a converter according to set components, removing harmful gas in the steel through RH vacuum refining treatment, decarbonizing, dephosphorizing and desulfurizing, and finally carrying out continuous casting to prepare a continuous casting billet; the continuous casting billet comprises, by mass, 0.001-0.008% of C, 1.5-4.8% of Si, 0.5-2% of Cu, 0.5-1.5% of Ni, 0.2-1% of Al, 0.2-1.5% of Mn, 0.005% of P, 0.005% of S, and the balance of Fe and inevitable impurities;
(2) placing the continuous casting slab in a soaking furnace, preserving heat at 850-1150 ℃, and then carrying out multi-pass hot rolling at 720-1080 ℃, wherein the interval time between two adjacent passes of hot rolling is 30-180 s; air cooling to room temperature after hot rolling to prepare a hot rolled plate;
(3) keeping the temperature of the hot rolled plate at 800-1150 ℃ for 30-180 min for normalizing, wherein the normalizing is performed under the condition of a nitrogen-hydrogen mixed atmosphere, and the volume concentration of hydrogen is 20-50%; then air-cooling to room temperature to obtain a normalizing plate;
(4) cold rolling the normalized plate for multiple times to prepare a cold-rolled plate;
(5) carrying out annealing treatment on the cold-rolled sheet at the temperature of 900-1150 ℃ for 1-15 min, wherein the annealing treatment is carried out under the condition of a nitrogen-hydrogen mixed atmosphere, and the volume concentration of hydrogen is 20-50%; then air-cooling to room temperature to prepare an annealing plate;
(6) preserving the temperature of the annealing plate at 500-700 ℃ for 5-45 min for aging treatment to separate out a nano Cu-rich phase, wherein the size of the separated phase is 1-10 nm; and then air-cooling to room temperature to obtain the high-magnetic-induction high-strength non-oriented electrical steel.
2. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel by step regulation and control according to claim 1, wherein in the step (1), the thickness of the continuous casting billet is 50-350 mm.
3. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel according to claim 1 through step-by-step regulation, wherein in the step (2), the heat preservation time is 30-150 min.
4. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel through step-by-step regulation and control according to claim 1, wherein in the step (2), the number of hot rolling passes is 5-20, the reduction rate of each pass is 5-20%, and the total reduction rate is 68-99.6%.
5. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel according to claim 1, wherein in the step (2), the thickness of the hot-rolled plate is 1.5-16 mm.
6. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel through step-by-step regulation and control according to claim 1, wherein in the step (4), the number of cold rolling passes is 6-30, the reduction rate of each pass is 5-15%, and the total reduction rate is 66.7-99.7%.
7. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel according to claim 1, wherein in the step (4), the thickness of the cold-rolled plate is 0.05-0.50 mm.
8. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel according to claim 1, wherein the ratio of the lambda texture component of the high-magnetic-induction high-strength non-oriented electrical steel is not less than 40%.
9. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel according to claim 1, wherein the tensile strength of the high-magnetic-induction high-strength non-oriented electrical steel is 770-820 MPa, and the yield strength of the high-magnetic-induction high-strength non-oriented electrical steel is 650-700 MPa.
10. The method for preparing the high-magnetic-induction high-strength non-oriented electrical steel according to claim 1, wherein the magnetic induction intensity B of the high-magnetic-induction high-strength non-oriented electrical steel is501.55 to 1.74T, and iron loss P10/400Is 11 to 27W/kg.
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| CN114606445A (en) * | 2022-05-10 | 2022-06-10 | 江苏省沙钢钢铁研究院有限公司 | Production method of non-oriented silicon steel, non-oriented silicon steel and application thereof |
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| CN114606445A (en) * | 2022-05-10 | 2022-06-10 | 江苏省沙钢钢铁研究院有限公司 | Production method of non-oriented silicon steel, non-oriented silicon steel and application thereof |
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