CN114411064B - High-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel and manufacturing method thereof - Google Patents
High-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention provides high-magnetic-induction high-strength cerium-containing non-oriented silicon steel and a manufacturing method thereof, wherein the high-magnetic-induction high-strength cerium-containing non-oriented silicon steel comprises the following components: c:0.001% -0.003%, si:2.00% -3.50%, al:0.70% -0.90%, mn:0.20% -0.45%, cu:1.00% -2.25%, ce: 0.005-0.010%, less than or equal to 0.005% of O, less than or equal to 0.007% of P + S, less than or equal to 0.005% of N, and the balance of Fe and inevitable impurities. Compared with the prior art, the invention fully exerts the functions of precipitation strengthening of copper, modification and inclusion of cerium, grain size regulation and control and texture improvement by alloying copper, cerium and the like and matching with proper rolling and heat treatment processes, develops the high-strength non-oriented electrical steel with excellent magnetic performance, and improves the strength of the non-oriented silicon steel on the premise of ensuring the magnetic performance.
Description
Technical Field
The invention belongs to the technical field of silicon steel manufacturing, and particularly relates to high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel and a manufacturing method thereof.
Background
The green development of energy conservation and environmental protection becomes one of the ideas of the current social development. Under the background, new energy automobiles become an inevitable trend of future development of automobiles, and mainly comprise hybrid electric automobiles and pure electric automobiles. One of their core components is the drive motor system.
The performance of the non-oriented silicon steel sheet as a key material of the driving motor influences the driving characteristics (electricity, kinetic energy conversion efficiency, acceleration and deceleration characteristics and the like) and service performance (noise, service life and the like) of the driving motor. Based on the light weight principle of new energy automobiles and the complexity of the working condition of a driving motor system, the driving motor for the automobiles is required to have the characteristics of high power density, large torque, wide working speed range, small volume, high efficiency and the like. The permanent magnet synchronous motor is an ideal choice for a driving motor of a new energy automobile, and the power (torque), the efficiency and the service life of the permanent magnet synchronous motor are greatly related to the magnetic property and the mechanical property of the used non-oriented silicon steel sheet. The magnetic performance determines the torque and the efficiency of the motor, the lower the iron loss of the silicon steel sheet, the higher the motor efficiency, and the larger the magnetic induction, the larger the motor torque is; the mechanical property determines the processing precision, the service bearing strength, the maximum rotating speed and the service life of the stator and the rotor. The development of high-strength high-efficiency non-oriented silicon steel has important significance for the development of new energy automobile industry, environmental protection, energy conservation and consumption reduction.
According to the service conditions, the silicon steel sheet for the new energy automobile driving motor needs to have good magnetic property and high strength at the same time, and the method specifically comprises the following steps: 1. the magnetic induction is high, so that good driving experience is guaranteed; 2. high magnetic induction under a medium-low magnetic field and low iron loss under high frequency so as to improve the energy conversion efficiency; 3. high enough strength to resist the centrifugal force when the motor rotor runs at high speed; 4. good punching property: the gap between the rotor and the stator can be reduced, so that the magnetic flux density is effectively improved; 5. high fatigue life to ensure that the silicon steel sheet rotating at high speed in service period can not generate fatigue failure in the service period of the automobile.
At present, the research and development work on the high-strength non-oriented silicon steel in China is less reported, and only a plurality of units such as Baowu group, saddle steel, northeast university, beijing technology university, iron and steel research institute and the like have open data to be searched. Baoku group Bao Steel, 2012, 5, 16 discloses high-strength non-oriented silicon steel with high magnetic induction and a manufacturing method thereof (CN 102453838A), wherein the strength is improved mainly by solid solution strengthening of Cr and Ni, the iron loss is reduced by controlling C, N, S and other elements harmful to the iron loss, and the magnetic induction is improved by a proper normalizing process. Two methods for producing high-strength non-oriented silicon steel by using a twin-roll thin-strip continuous casting technology are reported by northeast university (CN 106435358A published in 2 and 22 months in 2017 and CN106282781A published in 1 and 4 months in 2017), and the strengthening principle is realized by precipitation strengthening of Nb and Cu. Beijing university of science and technology discloses two methods of high-strength non-oriented silicon steel for a driving motor, one is CN107130169A which is disclosed in 2017, 9, month and 5, a high-strength copper-containing cold-rolled non-oriented silicon steel and a manufacturing method thereof, the high strength is realized by adding Cu and Ni, the increase of favorable texture components is promoted by adopting a secondary cold rolling process, and the generation of unfavorable texture is reduced to improve the magnetic induction; and CN107746941A disclosed in 2018, 3, month and 2, for a high-strength cold-rolled non-oriented silicon steel for a driving motor and a manufacturing method thereof, the strength is improved by adding Nb and Cr, texture components are increased by adopting secondary cold rolling, unfavorable texture production is reduced, and magnetic induction is improved. The institute of iron and steel has tried the high-strength non-oriented silicon steel in the laboratory by simulating the thin slab continuous casting and rolling technique. CN103882288A disclosed in 6, 25.2014.2014.A special high-strength cold-rolled non-oriented silicon steel and a production method thereof mainly improve the strength through solid solution strengthening.
The most developed and matured high-strength non-oriented silicon steel is japan in foreign countries, and since 1980, research on high-strength non-oriented silicon steel has been started, and representatives of the manufacturers mainly include new day iron, JFE, and sumitomo metals. The solid solution strengthening of Si, P, mn, and Ni is mainly used in the patent disclosed in the last 1990, but other alloying elements such as Cr, mo, cu, and Ti are sometimes used, and the grain size of the final plate is generally controlled appropriately to achieve high strength. Cr can effectively reduce high-frequency iron loss and has the function of reducing stress sensitivity. After 1990, other strengthening methods have been used in the new iron publication patent, and Nb, zr, ti, and V carbonitrides precipitation strengthening was used together with solid solution strengthening (2003-34268, 2008-050685), and in the last decade of the year, new iron was developed into high-strength non-oriented silicon steel (102007226 a) in which precipitation strengthening of Cu metal phase was changed. The Sumitomo metal provides a method for adding microalloy of Nb, ti, V and Zr strong carbonitride forming elements into non-oriented silicon steel, so that on one hand, fine carbide particles are formed, and the strength is improved through precipitation strengthening; on the other hand, recrystallization during annealing is inhibited by dissolving Nb in a solid solution, so that the recrystallization fraction does not exceed 90%, defects such as cold working dislocation of a part are reserved, the strength is not remarkably reduced due to recrystallization, and SXRC series high-strength non-oriented silicon steel (US 7,922,834B2) is developed. JFE improves the strength of non-oriented silicon steel by various methods such as solid solution strengthening (2008-156737, 2008-240104) of Si, cr, mn, ni, etc., precipitation strengthening (2004-315956, 2004-183066, 2004-300535, 2005-240150) of Cu, and dislocation strengthening (2007-186790).
In conclusion, the research and development of the high-strength non-oriented silicon steel are mainly based on the principles of solid solution strengthening, precipitation strengthening, dislocation strengthening and the like, but the strengthening methods are difficult to apply to the non-oriented silicon steel. The solid solution strengthening effect of P, mn, ni and Si is remarkable, and the deterioration of the magnetic property is relatively minimum; however, ni is expensive in alloy cost, P easily causes cold embrittlement, and Si is high to make the rolling process difficult and to reduce magnetic induction. The precipitation strengthening effect of Nb, V and Ti is remarkable, but a proper content of C, N needs to be reserved in steelmaking so as to be used for subsequent precipitation of Nb, V and Ti carbonitrides, the precipitation amount and the precipitation temperature are ensured to be proper, the production process window is narrow, higher requirements are provided for smelting and rolling, and the production difficulty is increased; and precipitation strengthening of carbonitride deteriorates magnetic induction by inhibiting the movement of magnetic domain walls. Although the dislocation strengthening by the incomplete recrystallization is economical, the effect of improving the strength is not significant and the iron loss is increased.
Therefore, the development of the non-oriented silicon steel with low alloy and process cost and excellent magnetic property and mechanical property is urgent, and the method has important significance for energy conservation, consumption reduction and environmental protection.
Disclosure of Invention
The invention aims to provide high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel and a manufacturing method thereof, which fully play the roles of precipitation strengthening of copper, modification and inclusion of cerium, grain size regulation and control and texture improvement by alloying copper and cerium and matching with appropriate heat treatment processes such as rolling, normalizing, annealing and the like, develop high-strength non-oriented electrical steel with excellent magnetic performance and improve the strength of the non-oriented silicon steel on the premise of ensuring the magnetic performance.
The specific technical scheme of the invention is as follows:
high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following components in percentage by mass:
c:0.001% -0.003%, si:2.00% -3.50%, al:0.70% -0.90%, mn:0.20% -0.45%, cu:1.00% -2.25%, ce: 0.005-0.010 percent of iron oxide, less than or equal to 0.005 percent of O, less than or equal to 0.007 percent of P + S, less than or equal to 0.005 percent of N, and the balance of Fe and inevitable impurities.
The high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following components in design thought: the requirements of the levels of impurity elements such as ultra-low carbon, medium silicon, low aluminum, low manganese, low oxygen, phosphorus, sulfur and the like aim to ensure good punching effect and effectively avoid copper brittleness on the premise of meeting the magnetic property and strength. The main functions of the alloy elements in the invention are as follows:
1) Carbon: solid solution strengthening effect. Carbon is one of the essential strengthening alloy elements in steel, but is not good for magnetic induction and iron loss, and the content of carbon in non-oriented silicon steel is usually reduced as much as possible due to smelting level and cost factors. In the invention, in the aspects of cost and strength, 0.001-0.003% of carbon is reserved under the principle of reducing the carbon content as much as possible.
2) Silicon and aluminum: reducing iron loss and improving hardness. Silicon and aluminum can obviously improve the resistivity, reduce eddy current loss, hysteresis loss and iron loss, and are main alloy elements for improving the grade of electrical steel. However, silicon increases the brittleness of steel, reduces the plasticity, and reduces the magnetic induction. Therefore, in order to ensure the iron loss and plastic workability of the non-oriented silicon steel, the contents of silicon and aluminum are respectively designed as follows: 2.00% -3.50% and 0.70% -0.90%.
3) Manganese: the austenite phase region is enlarged, the solid solution of copper is ensured, and the hot brittleness of the steel is avoided. Manganese sulfide is formed by manganese and sulfur, so that the hot brittleness phenomenon caused by ferrous sulfide with a low melting point formed along a grain boundary can be prevented; manganese improves hot rolling plasticity and hot rolled sheet texture because manganese expands the austenite phase region, not only increasing the amount of copper in solution to avoid hot embrittlement of the copper but also slowing the rate at which the austenite phase transforms to the ferrite phase. High manganese content, increased solid solution temperature of manganese sulfide, and can promote coarsening of manganese sulfideThe manganese can improve the texture, promote the strengthening of (100) and (110) components, weaken the (111) component and improve the magnetic performance. Generally, the Mn/S is required to be more than or equal to 10, and the lower the sulfur content is, the corresponding reduction of manganese can be realized. When manganese is more than 0.75%, A 3 The phase transition temperature is significantly reduced. Mn exceeding 1.5% by weight results in excessively low normalizing and final annealing temperatures, which is disadvantageous in magnetic properties and increases cost. Therefore, the manganese content is designed to be: 0.20 to 0.45 percent.
4) Cerium: modification and inclusion, adjustment of grain size and improvement of texture. The proper amount of cerium obviously reduces the number of fine inclusions (inclusions with the size of less than 1 mu m) in the non-oriented silicon steel, denatures the inclusions with irregular shapes such as aluminum nitride, aluminum oxide and the like into spherical or approximately spherical composite inclusions such as cerium sulfide, aluminum oxide, aluminum nitride, cerium sulfide, aluminum oxide and the like, and effectively inhibits the precipitation of manganese sulfide in the steel, thereby weakening the pinning effect on grain boundaries, promoting the growth of grains with the {100} and {110} orientation which are favorable for magnetism, and preventing the grains with the {111} and {112} orientation which are harmful for magnetism during annealing from preferentially nucleating in the vicinity of the inclusions such as the aluminum nitride, the manganese sulfide and the like. Excessive cerium generates excessive cerium oxysulfide and cerium sulfide inclusions, which not only enhances the grain boundary pinning force and prevents the crystal grains from growing during annealing, but also promotes the preferential nucleation of the crystal grains with {111} orientation which are harmful to the magnetic performance around the crystal grains, thereby deteriorating the magnetic performance. Therefore, the content of cerium is designed to be: 0.005-0.010%.
5) Copper: precipitation strengthening effect. Copper is an austenite stabilizing element, has larger solid solution amount (maximally more than 10%) in austenite, has small solid solution degree in ferrite, can effectively precipitate a copper metal phase along with the reduction of temperature, and has remarkable strengthening effect. In addition, the precipitation strengthening of copper in the ferrite phase does not impair the magnetic properties of the silicon steel sheet at the same time. However, copper tends to cause hot embrittlement of steel, and the content is not so high. Therefore, the content thereof is determined to be 1.00% to 2.25%.
The matrix structure of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel is 100% of polygonal ferrite, and the average grain size of the polygonal ferrite is 100-145 mu m;
the magnetic induction intensity of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steelDegree B 50 Greater than 1.65T, iron loss value P 1.5/50 ＝2.9-3.1W/kg，P 1.0/400 24.4-27.5W/kg, yield strength sigma 0.2 =581-780MPa, tensile strength sigma b =713-790MPa, and the elongation is 12-20.5%.
The invention provides a manufacturing method of high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel, which comprises the steps of smelting, pouring, hot rolling, normalizing, acid washing, cold rolling and annealing.
The smelting and smelting equipment can be one of a vacuum induction furnace, a converter or an electric furnace;
furthermore, rare earth cerium is added in the tapping process of molten steel, and the purity of the added rare earth cerium is 99.99 percent. In order to improve the yield of cerium and ensure the uniformity of cerium in steel, rare earth cerium is added in a mode that fine blocks with the size of 1-2mm are wrapped by pure iron skin.
The casting is one of continuous casting or die casting.
The hot rolling is carried out at the heating temperature of 1050-1200 ℃, the heat preservation time is 40-100min, the rolling pass is not less than five passes, the total rolling reduction is 76-92%, the reduction of each pass is 25-35%, and the thickness of the hot rolled plate finished product is controlled to be 2.25-2.65mm.
The normalizing treatment is carried out at 980-1020 ℃ for 3-5min under the protective atmosphere of pure nitrogen, pure argon or mixed gas of 1:1 in volume ratio of nitrogen to argon.
And in the cold rolling, the cold rolling reduction is controlled to be 73.3-84.9%, and the thickness of the cold rolled plate is 0.4-0.6mm.
The annealing is carried out at 900-1050 deg.C for 3-5min in an atmosphere of 30 vol% 2 And 70% of N 2 The annealing furnace may be one of a tube furnace, a bell-type furnace and a continuous annealing furnace.
The design idea and principle of the invention are as follows:
because of the low-carbon and low-nitrogen component characteristics of the non-oriented electrical steel and the structural characteristics of coarse and uniform crystal grains, solid solution strengthening, precipitation strengthening of carbonitride, fine grain strengthening and the like cannot be effectively used, and in comparison, precipitation strengthening of copper is one type of precipitation strengtheningAnd (4) comparing ideal selection. Firstly, because copper itself is an austenite stabilizing element, a large solid solution amount (maximum more than 10%) exists in austenite, and the solid solution degree is small in ferrite, a copper metal phase can be effectively precipitated along with the reduction of temperature, and the strengthening effect is remarkable. Secondly, compared with precipitation strengthening of titanium, niobium and the like, on one hand, the method avoids adding a large amount of manganese and nickel so as to form austenite phase at high temperature to dissolve carbide, so that the cost is relatively economic; on the other hand, because the steel is not strengthened by carbide and nitride precipitation, the steel does not need to reserve enough carbon content in the steel for subsequent precipitation, but directly obtains the ultra-low carbon content, and does not need to control the precipitation of carbide and nitride during hot rolling, coiling and annealing, thereby the process is relatively simple. Thirdly, the precipitation strengthening of copper in the ferrite phase does not damage the magnetic performance of the silicon steel sheet at the same time. Although copper is a relatively ideal strengthening phase, the problem of copper hot brittleness needs to be properly solved by utilizing precipitation strengthening of copper, and the problem of copper hot brittleness can be well solved by adopting the hot rolling heating temperature of 1050-1200 ℃ for avoiding precipitation of copper sulfide to ensure that the precipitation phase of copper is fully dissolved in the rolling process. In addition, the invention adds the rare earth element cerium with high chemical activity and proper content, has strong binding force with impurities such as oxygen, sulfur and the like in molten steel, and can not only give full play to the rectangular or strip-shaped inclusions such as modified aluminum nitride, aluminum oxide and the like of the molten steel to be spherical composite inclusions (CeO) 2 S 2 +AlN、CeS+CeAlO 3 And CeS + Al 2 O 3 ) And the function of aggregating and coarsening fine inclusions with the size less than 1 mu m (namely reducing the number of fine inclusions and increasing the number of coarse inclusions with the size of 2-5 mu m), and the function of regulating and controlling the grain size by modifying the inclusions, reducing the number of fine inclusions (with the size less than 1 mu m) and inhibiting the precipitation of manganese sulfide inclusions, improving the recrystallization nucleation and recrystallization grain texture types, improving the component strength of favorable surface textures {110} and {100} and reducing the component strength of gamma fiber textures, thereby improving the magnetic performance; and the regulation and control of the structure can generate mutual promotion effect with the precipitation strengthening of copper, thereby simultaneously improving the magnetic property and the strength. The concrete points are as follows: in one aspect, the addition of cerium results in ferriteThe lattice distortion is increased, and the precipitation of copper can be promoted, so that the strengthening effect is improved; on the other hand, the precipitation of copper can also hinder the growth of recrystallized grains to a certain degree, so that the size of ferrite grains is in a proper range, and the improvement of magnetic performance is facilitated. The normalizing and annealing process has important influence on the grain size, the number and the size of precipitated phases, and the grain size of ferrite with high normalizing and annealing temperature is coarser, so that the strength is reduced; the normalizing and annealing temperatures are low, recrystallization is insufficient, and the grain size is uniform, which is disadvantageous to this property. Therefore, the invention obtains the normalizing and annealing temperature process parameters matched with the components, and the alloy components influence the recrystallization temperature and the phase transformation point temperature, so that the optimal normalizing and annealing temperatures of the non-oriented silicon steel with different components are different.
In summary, the present invention is unique in the design of key alloy elements (cerium, copper, etc.), normalization, the formulation of annealing process parameters, microstructure control, etc. Compared with the prior art, the invention has the following technical effects: the optimized alloy components are designed and matched with reasonable process parameters, and the comprehensive performance of the product is more excellent. The addition of alloy elements is less, the conventional production process is adopted, the equipment investment is not required to be increased, and the production cost is low. The average grain size of the finished non-oriented silicon steel plate prepared by the invention is 100-145 mu m, and the magnetic induction intensity B 50 Greater than 1.65T, iron loss value P 1.5/50 ＝2.9-3.1W/kg，P 1.0/400 =24.4-27.5W/kg, yield strength sigma 0.2 =581-780MPa, tensile strength sigma b =713-790MPa, and the elongation is 12-20.5%.
Drawings
FIG. 1 is a metallographic structure drawing of a 950 ℃ annealed plate of high-magnetic-induction high-strength cerium-and-copper-containing non-oriented silicon steel of example 1;
FIG. 2 is a diagram showing the inclusion morphology of an annealed plate of high-magnetic-induction, high-strength, cerium-containing, copper-containing, non-oriented silicon steel of example 1 at 950 ℃;
FIG. 3 is a copper precipitated phase morphology chart of a 950 ℃ annealed sheet of the high magnetic induction high strength cerium-containing copper-containing non-oriented silicon steel of example 1;
FIG. 4 is a metallographic structure drawing of an annealed sheet of cerium-containing, copper-containing, non-oriented silicon steel of example 2 having a high magnetic induction and a high strength at 1000 ℃;
FIG. 5 is a metallographic structure drawing of an annealed sheet of high-magnetic-strength cerium-containing and copper-containing non-oriented silicon steel of example 3 at 1050 ℃.
Detailed Description
The present invention will be described in detail with reference to specific examples, but the present invention is not limited to the examples.
Example 1
High-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following components in percentage by mass:
c:0.003%, si:2.80%, al:0.87%, mn:0.32%, cu:2.24%, ce:0.0077%, O is less than or equal to 0.003%, P + S:0.006%, N:0.003% and the balance of Fe and inevitable impurities.
The manufacturing method of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following steps: the finished plate is prepared by smelting in a vacuum induction furnace, casting by a cast iron die, hot rolling, normalizing, acidity, cold rolling and annealing.
Specifically, the method comprises the following steps: rare earth cerium (with the purity of 99.99%) is added in the tapping process of molten steel, and is added in a mode that fine blocks with the size of 1-2mm are wrapped by pure iron skin in order to improve the yield and ensure the uniformity of cerium in steel. Tapping and casting to form a casting blank, wherein the tapping temperature is 1600 ℃.
And (3) preserving the temperature of the casting blank in a heating furnace at 1150 ℃ for 90 mm, performing five times of hot rolling with controlled reduction, wherein the reduction rate of each time of the first three times is 20%, the reduction rate of each time of the second two times is 13%, and performing hot rolling to obtain a hot rolled plate with the thickness of 2.5mm, wherein the final rolling temperature is 870 ℃. And (3) preserving the heat of the hot rolled plate at 1000 ℃ for 5min under the pure nitrogen protective atmosphere, and then air-cooling to room temperature to obtain the normalized plate. And performing acid pickling treatment on the normalized plate to remove iron scales, and then cold-rolling the normalized plate to 0.5mm. Annealing the cold-rolled sheet to obtain an annealed sheet product at 950 deg.C for 5min in an atmosphere of 30% by volume 2 +70％N 2 The mixed gas of (1).
The average grain size of the finished product plate of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel is 100 mu m, and the magnetic induction intensity B 50 =1.655T, iron loss value P 1.5/50 ＝3.047W/kg，P 1.0/400 =27.250W/kg, yield strength sigma 0.2 =693MPa, tensile Strength σ b =784MPa, elongation 18%.
Example 2
High-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following components in percentage by mass:
c:0.003%, si:2.90%, al:0.88%, mn:0.32%, cu:1.24%, ce:0.0078%, O is less than or equal to 0.005%, P + S:0.005%, N:0.002%, and the balance of Fe and inevitable impurities.
The manufacturing method of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following steps: the finished plate is prepared by smelting in a vacuum induction furnace, casting by a cast iron die, hot rolling, normalizing, acidity, cold rolling and annealing.
Specifically, the method comprises the following steps: rare earth cerium (with the purity of 99.99%) is added in the tapping process of molten steel, and is added in a mode that fine blocks with the size of 1-2mm are wrapped by pure iron skin in order to improve the yield and ensure the uniformity of cerium in steel. Tapping and casting to form a casting blank, wherein the tapping temperature is 1600 ℃.
And (3) preserving the temperature of the casting blank in a heating furnace at 1150 ℃ for 90min, then carrying out five-pass hot rolling with controlled reduction, wherein the reduction rate of each pass of the first three passes is 20%, the reduction rate of each pass of the second two passes is 13%, and carrying out hot rolling to obtain a hot rolled plate with the thickness of 2.5mm, wherein the final rolling temperature is 870 ℃. And (3) preserving the heat of the hot rolled plate at 1020 ℃ for 3min under the pure nitrogen protective atmosphere, and then air-cooling to room temperature to obtain the normalized plate. And after the normalizing plate is subjected to acid pickling treatment to remove iron scales, cold rolling to 0.5mm. Annealing the cold-rolled sheet to obtain an annealed sheet product at 1000 deg.C for 5min in an atmosphere of 30% by volume 2 +70％N 2 The mixed gas of (2).
The average grain size of the finished plate of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel is 120 mu m. Magnetic induction B 50 =1.652T, iron loss value P 1.5/50 ＝2.929W/kg，P 1.0/400 =25.629W/kg, yield strength sigma 0.2 =654MPa, tensile strength sigma b =735MPa, elongation 15%.
Example 3
High-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following components in percentage by mass:
c:0.003%, si:2.90%, al:0.88%, mn:0.32%, cu:1.24%, ce:0.0078%, O is less than or equal to 0.005%, P + S:0.005%, N:0.002%, and the balance of Fe and inevitable impurities.
The manufacturing method of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel comprises the following steps: the finished plate is prepared by smelting in a vacuum induction furnace, casting by a cast iron die, hot rolling, normalizing, acidity, cold rolling and annealing.
Specifically, the method comprises the following steps: rare earth cerium (with the purity of 99.99%) is added in the tapping process of molten steel, and is added in a mode that fine blocks of 1-2mm are wrapped by pure iron sheets in order to improve the yield and ensure the uniformity of cerium in steel. Tapping and casting to form a casting blank, wherein the tapping temperature is 1600 ℃.
And (3) keeping the temperature of the casting blank in a heating furnace at 1150 ℃ for 90min, performing five-pass hot rolling with controlled reduction, wherein the reduction rate of each pass of the first three passes is 20%, the reduction rate of each pass of the second two passes is 13%, and performing hot rolling to obtain a hot rolled plate with the thickness of 2.5mm, wherein the final rolling temperature is 870 ℃. And (3) preserving the heat of the hot rolled plate at 1020 ℃ for 3min under the pure nitrogen protective atmosphere, and then air-cooling to room temperature to obtain the normalized plate. And after the normalizing plate is subjected to acid pickling treatment to remove iron scales, cold rolling to 0.5mm. Annealing the cold-rolled sheet to obtain an annealed sheet product at 1050 deg.C for 3min in an atmosphere of 30% by volume 2 +70％N 2 The mixed gas of (1).
The average grain size of the finished plate of the high-magnetic-induction high-strength cerium-containing copper-containing non-oriented silicon steel is 135 mu m. Magnetic induction B 50 =1.663T, iron loss value P 1.5/50 ＝2.921W/kg，P 1.0/400 =25.638W/kg, yield strength sigma 0.2 =581MPa, tensile strength σ b =713MPa, elongation 20%.
Comparative example 1
High-magnetic-induction high-strength cerium-containing non-oriented silicon steel comprises the following components in percentage by mass:
c:0.004%, si:2.89%, al:0.89%, mn:0.20%, ce:0.0055%, O is less than or equal to 0.005%, P + S:0.005%, N:0.002%, and the balance of Fe and inevitable impurities.
The manufacturing method of the high-magnetic-induction high-strength cerium-containing non-oriented silicon steel comprises the following steps: the finished plate is prepared by smelting in a vacuum induction furnace, casting by a cast iron die, hot rolling, normalizing, acidity, cold rolling and annealing.
Specifically, the method comprises the following steps: rare earth cerium (with the purity of 99.99%) is added in the tapping process of molten steel, and is added in a mode that fine blocks with the size of 1-2mm are wrapped by pure iron skin in order to improve the yield and ensure the uniformity of cerium in steel. Tapping and casting to form a casting blank, wherein the tapping temperature is 1600 ℃.
And (3) keeping the temperature of the casting blank in a heating furnace at 1150 ℃ for 90min, performing five-pass hot rolling with controlled reduction, wherein the reduction rate of each pass of the first three passes is 20%, the reduction rate of each pass of the second two passes is 13%, and performing hot rolling to obtain a hot rolled plate with the thickness of 2.5mm, wherein the final rolling temperature is 870 ℃. And (3) keeping the temperature of the hot rolled plate at 1000 ℃ for 4min under the pure nitrogen protective atmosphere, and then air-cooling to room temperature to obtain the normalized plate. And after the normalizing plate is subjected to acid pickling treatment to remove iron scales, cold rolling to 0.5mm. Annealing the cold-rolled sheet to obtain an annealed sheet product at 1020 ℃ for 5min in an atmosphere of 30% by volume 2 +70％N 2 The mixed gas of (1).
The average grain size of the finished plate of the high-magnetic-strength cerium-containing non-oriented silicon steel is 155 mu m. Magnetic induction B 50 =1.683T, iron loss value P 1.5/50 ＝3.111W/kg，P 1.0/400 =27.358W/kg, yield strength sigma 0.2 =483MPa, tensile Strength σ b =619MPa, elongation 25%.
It can be seen from the cases of examples 1 to 3 and comparative example 1 that, in the case where the carbon content is not more than 0.003% and cerium and copper are contained at the same time, the magnetic properties and strength of the non-oriented silicon steel are well matched, especially the strength is significantly higher than that of the steel containing cerium alone and the carbon content is more than 0.003%. This is that the nano-copper precipitated phase (shown in fig. 3) has a significant strengthening effect and does not significantly reduce the magnetic performance; and cerium modified inclusions (shown in FIG. 2), and a combination of the effects of reducing the number of fine inclusions with a size of less than 1 μm and increasing the number of coarse inclusions with a size of 2 to 5 μm in order to improve magnetic properties.
Claims (4)
1. The high-magnetic-induction high-strength cerium-containing non-oriented silicon steel is characterized by comprising the following components in percentage by mass:
c:0.001% -0.003%, si:2.00% -3.50%, al:0.70% -0.90%, mn:0.20% -0.45%, cu:1.00% -2.25%, ce: 0.005-0.010%, less than or equal to 0.005% of O, less than or equal to 0.007% of P + S, less than or equal to 0.005% of N, and the balance of Fe and inevitable impurities;
the average grain size of the high-magnetic-induction high-strength cerium-containing non-oriented silicon steel is 100-145 mu m;
the production method of the cerium-containing non-oriented silicon steel with high magnetic induction and high strength comprises the steps of smelting, pouring, hot rolling, normalizing, pickling, cold rolling and annealing;
adding rare earth cerium during tapping of molten steel, wherein the purity of the added rare earth cerium is 99.99%; rare earth cerium is added in a mode that fine blocks with the diameter of 1-2mm are wrapped by pure iron sheets;
the normalizing treatment temperature is 980-1020 ℃ and the time is 3-5min; the normalizing treatment is carried out under the protective atmosphere of pure nitrogen, pure argon or mixed gas with the volume ratio of the nitrogen to the argon of 1:1;
magnetic induction intensity B of high-magnetic-induction high-strength cerium-containing non-oriented silicon steel 50 Greater than 1.65T, iron loss value P 1.5/50 ＝2.9-3.1W/kg，P 1.0/400 24.4-27.5W/kg, yield strength sigma 0.2 =581-780MPa, tensile strength sigma b =713-790MPa, and the elongation is 12-20.5%.
2. The high magnetic induction high strength cerium-containing non-oriented silicon steel as claimed in claim 1, wherein the hot rolling is carried out at 1050-1200 ℃ for 40-100min.
3. The high magnetic induction high strength cerium-containing non-oriented silicon steel as claimed in claim 1, wherein the cold rolling is performed with a cold rolling reduction controlled to 73.3% -84.9%.
4. The high magnetic induction high strength cerium-containing non-oriented silicon steel as claimed in claim 1, wherein the annealing temperature is 900-1050 ℃ and the annealing time is 3-5min.
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