CN115216694B - High-strength non-oriented silicon steel thin strip with excellent magnetic performance for automobile driving motor and manufacturing method thereof - Google Patents
High-strength non-oriented silicon steel thin strip with excellent magnetic performance for automobile driving motor and manufacturing method thereof Download PDFInfo
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- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 67
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 33
- 238000000137 annealing Methods 0.000 claims abstract description 46
- 238000000034 method Methods 0.000 claims abstract description 46
- 238000005097 cold rolling Methods 0.000 claims abstract description 38
- 238000001953 recrystallisation Methods 0.000 claims abstract description 26
- 238000005096 rolling process Methods 0.000 claims abstract description 24
- 238000001816 cooling Methods 0.000 claims abstract description 19
- 239000012535 impurity Substances 0.000 claims abstract description 10
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- 229910052742 iron Inorganic materials 0.000 description 22
- 238000001556 precipitation Methods 0.000 description 13
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- 238000005266 casting Methods 0.000 description 10
- 238000005098 hot rolling Methods 0.000 description 10
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- 238000003723 Smelting Methods 0.000 description 6
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- 229910000838 Al alloy Inorganic materials 0.000 description 1
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- 229910000676 Si alloy Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
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- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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Abstract
The invention provides non-oriented silicon steel, which comprises the following components in percentage by weight: 0.001wt% to 0.003wt% of C, less than or equal to 0.001wt% of S, less than or equal to 0.003wt% of N, less than or equal to 0.001wt% of Ti, 3.1 to 3.5wt% of Si, 0.7 to 1.3wt% of Al, 0.1 to 1.0wt% of Mn, 0.8 to 1.7wt% of Cu, less than or equal to 0.02wt% of P, less than or equal to 0.003wt% of V, less than or equal to 0.002wt% of Zr, and the balance of Fe and unavoidable impurities. The invention also provides a manufacturing method of the non-oriented silicon steel, which comprises the following steps: carrying out normalizing acid washing treatment on the hot rolled coil to obtain a normalizing coil; performing warm rolling on the normalized coil by adopting a secondary cold rolling method to obtain a cold-rolled coil; the cold rolled coil is subjected to recrystallization annealing and cooling to obtain an annealed coil; the annealed coil is aged and cooled. The non-oriented silicon steel has excellent magnetic performance and high strength, and meets the requirements of an automobile driving motor. The manufacturing method of the invention has low cost and can realize industrial production.
Description
Technical Field
The invention relates to the technical field of silicon steel production, in particular to high-strength non-oriented silicon steel for an automobile driving motor and a manufacturing method thereof.
Background
With the development of the new energy automobile industry, the drive motor as a heart component of the new energy automobile starts to develop to high speed, high power density and miniaturization, and the silicon steel material is required to have the characteristics of low iron loss, high magnetic induction, high strength, high product thickness precision and the like at high frequency, and the material is required to be further thinned. Currently, an interior permanent magnet synchronous motor has become a mainstream of an electric automobile driving motor at high power density and high efficiency, and in order to achieve high efficiency, in general, a stator of the driving motor is required to have good magnetic performance, and a rotor has high-strength mechanical performance. The permanent magnet synchronous motor is narrower in magnetic bridge of the rotor core, is influenced by centrifugal force during high-speed rotation, is concentrated in stress, is easy to fatigue and even break after long-time service, and causes potential safety hazard, so that the rotor core needs high-strength silicon steel material to support to meet stress damage caused by high-speed rotation. However, conventional methods for increasing yield strength generally damage magnetic properties, resulting in a reduction in overall efficiency of the motor. Therefore, it has become a hot subject of current research to increase the yield strength of materials without damaging or even increasing the magnetic properties of the materials.
In the current electrical steel products, the yield strength of part of top grade brand products reaches 450Mpa by improving the Si content in the traditional process, and the rotating speed requirement of a common driving motor can be met. The driving motor has higher requirements on the strength of the material when running at an ultra-high speed (18000 r/min). The difficulty of the production process is greatly improved by continuously improving the Si content, and the magnetic performance, particularly the magnetic induction intensity, is continuously deteriorated. How to greatly improve the material strength without deteriorating the magnetic property and realize the industrial production becomes the direction of developing the silicon steel for the driving motor at the present stage.
Generally, the material strengthening mechanism is classified into fine-grain strengthening, solid solution strengthening, precipitation strengthening, and work hardening. Because the silicon steel has extremely low carbon content and finally completely recrystals and anneals to ensure the iron loss, the silicon steel cannot be strengthened by phase transformation and dislocation, and the feasible modes only include solid solution strengthening, precipitation strengthening and the like. A large number of domestic and foreign patents disclose the improvement of the yield strength of electrical steel in a solid solution strengthening and precipitation strengthening mode.
The Chinese patent application with publication number of CN111471941A discloses high-strength non-oriented silicon steel with yield strength of 600Mpa for driving motor rotor of new energy automobile and a manufacturing method thereof. Wherein, sn or Sb is added, any two elements of Cr, nb, ti, ni and V are added at the same time, and the hot rolling temperature, the normalizing speed, the recrystallization annealing temperature and the recrystallization annealing time are controlled to prepare the non-oriented silicon steel with the yield strength of 600Mpa grade and used for driving the motor rotor of 0.27mm-0.35 mm. The method has the advantages of short process flow, more added elements and high production cost; in terms of performance, although the obtained material has higher magnetic induction and strength, the medium-frequency iron loss is 22.6-30.4W/kg with P1.0/400, and the performance is general.
The Chinese patent application with publication number of CN107746941A discloses a high-strength cold-rolled non-oriented silicon steel for a driving motor and a manufacturing method thereof. The magnetic induction intensity, the iron loss and the yield strength of the prepared non-oriented silicon steel are balanced by controlling the secondary cold rolling reduction rate and the annealing process, but the method mainly utilizes a dislocation strengthening mechanism, and crystal grains are not fully grown after annealing, so that the magnetic property P1.0/400 is 18.8-32.12W/kg, and the performance is general.
The Chinese patent application with publication number of CN 112375965 discloses a preparation method of Cu-containing high-strength low-iron-loss non-oriented high-silicon steel. The method is characterized in that Cu is added, and a hot rolling solution treatment method, a medium-temperature rolling method, a recrystallization annealing method and an aging treatment method are adopted, so that the high-strength non-oriented silicon steel with excellent iron loss, magnetic induction and strength is invented in a laboratory, but the method is easy to generate thermal embrittlement in actual production when the Cu content is high, the hot rolling solution temperature and the recrystallization annealing time are too long, industrial production cannot be realized, the component range is wider, the performance may be unstable, and the performance reproducibility is poor.
The Chinese patent application with publication number of CN107130169A discloses a high-strength copper-containing cold-rolled non-oriented silicon steel and a manufacturing method thereof. Wherein, by adding trace elements such as Cu, ni and the like and controlling the secondary cold rolling reduction and the secondary annealing process, the high-strength copper-containing non-oriented silicon steel is obtained, although strongThe degree is higher up to 800Mpa, but the magnetic induction intensity and the medium frequency iron loss are general, B 5000 1.64-1.66T, and P1.0/400 is 20.04-25.04W/kg; in addition, the method adds noble metal Ni element to obviously raise the comprehensive cost.
The Chinese patent application with publication number of CN110004381A discloses a high-strength non-oriented silicon steel strip and a preparation method thereof. Wherein, cu and Cr elements are added, and the recrystallization annealing temperature and time are controlled to prepare the non-oriented silicon steel thin strip with low medium frequency iron loss, high magnetic induction and 600-700 megapascals strength. The method has the advantages of short process flow, relatively low cost, high cold rolling brittleness after Cu and Cr are added, high production difficulty, no description of the solution, long recrystallization annealing temperature period, low production efficiency and no contribution to realizing industrial continuous production.
Disclosure of Invention
The invention aims at overcoming the defects of the prior art and provides high-strength non-oriented silicon steel for an automobile driving motor and a manufacturing method thereof.
Specifically, the invention is realized by the following technical scheme:
a non-oriented silicon steel comprising, in weight percent: 0.001 to 0.003 weight percent of C, less than or equal to 0.001 weight percent of S, less than or equal to 0.003 weight percent of N, less than or equal to 0.001 weight percent of Ti, 3.1 to 3.5 weight percent of Si, 0.7 to 1.3 weight percent of Al, 0.1 to 1.0 weight percent of Mn, 0.8 to 1.7 weight percent of Cu, less than or equal to 0.02 weight percent of P, less than or equal to 0.003 weight percent of V, less than or equal to 0.002 weight percent of Zr, and the balance of Fe and unavoidable impurities.
Optionally, the non-oriented silicon steel comprises, in weight percent: 0.001wt% to 0.003wt% of C, less than or equal to 0.001wt% of S, less than or equal to 0.001wt% of Ti, 3.3 to 3.5wt% of Si, 0.8 to 1.0wt% of Al, 0.2 to 0.5wt% of Mn, 0.8 to 1.7wt% of Cu, 0.005 to 0.015wt% of P, less than or equal to 0.002wt% of V, less than or equal to 0.0015wt% of Zr, less than or equal to 0.003wt% of N, and the balance of Fe and unavoidable impurities.
Optionally, the sum of the contents of C, S, N and Ti satisfies C+S+N+Ti to be 80ppm or less.
Preferably, the sum of the contents of C, S, N and Ti satisfies C+S+N+Ti.ltoreq.50 ppm.
Optionally, the high-frequency iron loss P1.0/800 of the non-oriented silicon steel is 27-39W/kg, the magnetic induction B5000 is 1.67-1.72T, and the yield strength Rp0.2 is 560-720 Mpa.
A method for manufacturing non-oriented silicon steel, comprising:
(1) Carrying out normalizing acid washing treatment on the hot rolled coil to obtain a normalizing coil;
(2) Performing warm rolling on the normalized coil by adopting a secondary cold rolling method to obtain a cold-rolled coil;
(3) The cold rolled coil is subjected to recrystallization annealing and cooling to obtain an annealed coil;
(4) The annealed coil is aged and cooled.
Optionally, in the step (1), the hot rolled coil is subjected to normalizing pickling under the condition of protective atmosphere, wherein the normalizing temperature is 950-1050 ℃, and the normalizing speed is less than or equal to 20m/min.
Optionally, in the step (2), the rolling temperature is 300-450 ℃, the rolling reduction of the first cold rolling is 60-75%, then the intermediate annealing is performed at 850-1000 ℃, and then the second cold rolling is performed, wherein the rolling reduction is 40-65%.
Optionally, in step (3), the recrystallization anneal is performed at H 2 And N 2 The temperature of the recrystallization annealing is 900-1050 ℃ and the time of the recrystallization annealing is 3-10 min.
Optionally, in the step (4), the annealing coil is subjected to ageing treatment in a bell-type furnace, wherein the temperature of the ageing treatment is 300-500 ℃, and the ageing treatment time is 30-150 min.
According to the technical scheme, the high-strength non-oriented silicon steel for the automobile driving motor and the manufacturing method thereof have at least the following advantages:
the manufacturing method has the advantages of relatively simple process and low production cost, and can realize industrial production.
In the present invention, by adding a certain amount of Cu element to a high Si component and adopting a short-time recrystallization annealing and precipitation strengthening method, the obtained non-oriented silicon steel has high strength, excellent magnetic properties and excellent motor comprehensive efficiency.
Detailed Description
The present invention will be described in detail with reference to the following embodiments for a full understanding of the objects, features, and effects of the present invention. The process of the present invention is carried out by methods or apparatus conventional in the art, except as described below. Unless otherwise indicated, terms used in the present invention have meanings commonly understood by those skilled in the art.
Aiming at the defects of the existing non-oriented silicon steel, the inventor of the invention carries out intensive research on two aspects of element composition and manufacturing process, thereby providing the following design concept:
the method has the advantages that main alloy elements such as Si and Al are designed to be higher, steel purity and harmful elements such as C, S, N, ti, zr, V are reduced, a certain amount of Cu elements are added, meanwhile, the manufacturing process is improved, the primary cold rolling reduction rate, the secondary medium-temperature cold rolling process and technological parameters such as normalizing, intermediate annealing, recrystallization annealing temperature and speed are reasonably designed, and Cu is separated out through ageing treatment. By means of the synergistic effect of the element composition and the process, the magnetic performance and strength of the non-oriented silicon steel are improved.
Based on the above conception, the invention provides non-oriented silicon steel and a manufacturing method thereof.
In a first aspect, the invention provides non-oriented silicon steel, which comprises the following components in percentage by weight:
C 0.001wt％～0.003wt％；
S≤0.001wt％；
N≤0.003wt％；
Ti≤0.001wt％；
3.1 to 3.5wt% of Si, preferably 3.3 to 3.5wt%;
0.7 to 1.3wt% Al, preferably 0.8 to 1.0wt%;
mn 0.1wt% to 1.0wt%, preferably 0.2wt% to 0.5wt%;
Cu 0.8wt％～1.7wt％；
p is less than or equal to 0.02wt percent, preferably 0.005wt percent to 0.015wt percent;
v is less than or equal to 0.003wt%, preferably V is less than or equal to 0.002wt%;
zr is less than or equal to 0.002wt%, preferably Zr is less than or equal to 0.0015wt%;
the balance being Fe and unavoidable impurities.
In the invention, the sum of the content of C, S, N and the content of Ti in the non-oriented silicon steel meets the condition that C+S+N+Ti is less than or equal to 80ppm, preferably C+S+N+Ti is less than or equal to 50ppm.
The non-oriented silicon steel can realize synergistic effect by means of elements and the content thereof. The high-frequency iron loss is reduced by improving the resistivity of the finished product through the solid solution strengthening effect of the higher Si and Al alloy components. Meanwhile, a certain amount of Cu element is added under the higher Si component, the yield strength of the material is improved by the precipitation strengthening superposition effect of the high Si component and the Cu-containing steel, the yield strength can be improved to the centrifugal force requirement that the iron core rotor can rotate at a high speed (more than 18000 r/min), the resistivity can be improved, the high-frequency iron loss can be reduced, and the magnetic induction is not damaged. The actions of the elements are as follows:
1) C, N, S, ti is a hazardous element. The existence of the C, N is easy to cause precipitation of the carbide and the nitride, hurt the magnetic performance of the steel plate, and meanwhile, when the content of C is large, the silicon steel can generate magnetic aging, and the side crack of the hot rolled plate is easy to be caused, so that the quality and the production efficiency of the silicon steel are not guaranteed; the fine sulfide formed by S prevents the growth of crystal grains, and when the sulfur content is reduced, the iron loss is obviously reduced; tiN and TiC formed by Ti strongly prevent the growth of crystal grains, and particularly have bad influence on high-grade iron loss. Therefore, the invention reduces the content of elements affecting the purity of the steel as much as possible, and requires that C0.001wt% -0.003 wt%, S is less than or equal to 0.001wt%, ti is less than or equal to 0.001wt%, and C+S+N+Ti is less than or equal to 80ppm; more preferably, C+S+N+Ti is not more than 50ppm.
2) Si is an element for improving resistivity, and increasing Si can reduce iron loss, and meanwhile strength can be obviously improved, but after Si content is improved to a certain degree, a product becomes brittle, and magnetic induction is reduced, so that 3.1-3.5 wt% of Si is required, and 3.3-3.5 wt% is further preferred; al has similar effect with Si, can reduce the iron loss of steel and improve the magnetic performance of steel, and also properly improves the strength, but as Al increases, the viscosity of molten steel increases, the difficulty of steelmaking increases, and the magnetic induction also decreases, so that the Al content is required to be 0.7-1.3 wt%, and preferably 0.8-1 wt% of Al; mn increases the resistivity and also slightly increases the strength of the steel, but to a lesser extent than Si, al, while Mn can improve the hot rolled sheet structure, hot rolling plasticity and sheet formability, thus requiring 0.1 to 1wt% Mn, preferably 0.2 to 0.5wt%; cu can obviously enhance the strength of non-oriented silicon steel, the solubility of Cu in ferrite is very small, a large number of tiny and dispersed precipitated phases can be obtained by aging after solution treatment, the method has flexible hot rolling process control window, the operation is simple and cost-effective, the Cu precipitation can also increase the beneficial {110} texture strength and reduce the harmful {111} texture strength, so that the iron loss of an annealed plate is reduced, and the magnetic induction is not obviously deteriorated. Therefore, the Cu content in the present invention is designed to be 0.8 to 1.7wt%. Through reasonably designing the combination content ratio of Si, al, cu and Mn elements, the yield strength can be greatly improved, and the lower iron loss of the silicon steel at high frequency can be ensured without damaging the magnetic induction.
In a second aspect, the present invention provides a method for manufacturing non-oriented silicon steel, comprising:
(1) And (5) carrying out normalized pickling treatment on the hot rolled coil.
The hot rolled coil may be prepared by known methods, for example, smelting, RH vacuum treatment and casting of the elemental composition according to the first aspect of the invention, heating the resulting cast slab to 1100-1200 ℃, maintaining the temperature for about 60 minutes, and rapidly hot rolling to a hot rolled coil of 1.0-2.0 mm thickness, ensuring that Cu is sufficiently solutioned without precipitation or with a small amount of precipitation.
The normalized pickling treatment of the hot rolled coil is carried out under a protective atmosphere, for example, a pure nitrogen protective atmosphere. The normalizing temperature is 950-1050 deg.c and normalizing speed less than 20m/min. After the normalizing treatment, the product was sufficiently pickled with concentrated hydrochloric acid having a concentration of 20%, and then rapidly cooled to room temperature to obtain a normalized coil.
(2) Warm rolling by secondary cold rolling method
The intermediate temperature rolling temperature is 300-450 ℃, wherein the reduction of the first cold rolling is 60-75%, then the intermediate annealing is performed at 850-1000 ℃, then the second cold rolling is performed, the reduction is 40-65%, for example, for a hot rolled coil with a thickness of 1.0-2.0 mm, the thickness of the cold rolled coil subjected to the second cold rolling is 0.20-0.30 mm. The intermediate-temperature rolling can ensure that the rolling is smooth and the frequency of strip breakage is reduced under the condition of high alloy components, and the cold rolling yield is high; the reasonable design of the rolling reduction of two times and the intermediate annealing temperature ensures that the finished product has favorable textures such as {110}, {100} with high components and excellent magnetic performance.
(3) Recrystallization annealing
Cold rolled coil at H 2 And N 2 The volume ratio of (1:1) is greater than 900 ℃ to 1050 ℃ for recrystallization annealing, the annealing time is 3min to 10min, then the annealing is rapidly cooled at the speed of 50 ℃/s to 80 ℃/s, the coating is coated and coiled, firstly, the Cu is ensured to be fully dissolved and not precipitated, and secondly, the grain size of the obtained annealed coil is large, and the high-frequency iron loss is low.
(4) Aging treatment
And (3) sending the prepared annealed coil into a bell-type furnace for ageing treatment, wherein the ageing temperature is 300-500 ℃, the ageing time is 30-150 min, the uniform precipitation and the dispersion of epsilon-Cu phase are ensured, the strength is obviously improved, and then the annealing coil is air-cooled to room temperature, so that the high-strength non-oriented silicon steel with excellent magnetic property is obtained.
On the basis of improving the element composition of the non-oriented silicon steel, the invention optimizes the process so as to enable the process to be matched with the element composition, thereby improving the performance of the non-oriented silicon steel. The manufacturing method of the invention ensures the magnetic induction intensity through the technological means of high temperature normalization, secondary cold rolling, medium temperature rolling and the like, reduces the risk of cold rolling belt breakage, ensures the yield and improves the stability of the production process; the strength and excellent iron loss of the non-oriented silicon steel thin strip are ensured by means of high-temperature recrystallization annealing, rapid cooling and low-temperature aging, and the material strength requirement and the motor comprehensive efficiency requirement can be met simultaneously. The method comprises the following steps:
the method prevents the cooling precipitation of the fine dispersed second phase by controlling C, S, N, ti and other elements affecting the purity of the steel and controlling the content of Zr, V and other harmful elements during smelting, and is particularly beneficial to preventing the precipitation strengthening effect of Cu in the aging treatment process; because the solid solubility of Cu element in austenite is much larger than that in ferrite, the Cu element is subjected to high-temperature normalizing, recrystallization annealing and rapid water quenching cooling, the Cu element is basically completely dissolved in solid and is little in precipitation, and the subsequent aging is sufficient to obtain a uniformly distributed dispersed structure (mainly epsilon-Cu phase) without damaging the magnetic performance; the secondary cold rolling method is adopted during cold rolling, the reasonable cold rolling reduction rate and the intermediate annealing temperature are designed to improve the proportion of comprehensive favorable textures (cube textures and Goss textures), and the obtained finished product has high magnetic induction; because a certain amount of Cu element is added, the cold rolling production process is unstable and difficult, hot shortness and cracks are easy to occur when the steel plate is rolled, the rolling reduction is reasonably distributed through twice cold rolling, and the occurrence probability of cold rolling broken strips can be effectively reduced by adopting a medium-temperature rolling method, so that the rolling process is smoothly implemented. By comprehensively utilizing the multiple control means, the high-strength non-oriented silicon steel thin strip with excellent magnetic property for the automobile driving motor can be prepared.
Examples
The sources of the respective substances used in the examples are described below, and the raw materials and instruments used are commercially available, and are those conventionally used in the art, if not specifically described, as long as they meet the experimental requirements.
Example 1:
elemental composition of the non-oriented silicon steel strip of this embodiment: 0.003wt% of C, 0.001wt% of S, 0.001wt% of N, 0.0008wt% of Ti, 3.2wt% of Si, 0.8wt% of Al, 0.35wt% of Mn, 1.3wt% of Cu, 0.015wt% of P, 0.0015wt% of V and 0.001wt% of Zr, wherein the total content of C+S+N+Ti is less than or equal to 80ppm; the balance of Fe and unavoidable impurities.
The manufacturing method of the non-oriented silicon steel thin strip in the embodiment comprises the following steps:
smelting, RH vacuum treatment and casting according to the above components, heating a casting blank to 1150 ℃, preserving heat for 1h, and rapidly hot-rolling to a hot-rolled coil with the thickness of 1.8 mm; normalizing the hot rolled coil in pure nitrogen protective atmosphere, maintaining the normalizing temperature at 1000 ℃ and the speed at 15m/min, and then rapidly cooling to room temperature; the two times of cold rolling of the normalizing coil are carried out by adopting medium temperature rolling at 400 ℃, the primary cold rolling reduction is 75 percent, the intermediate annealing temperature is 960 ℃, and the secondary cold rolling is carried out to obtain a cold-rolled coil with the thickness of 0.20 mm;H 2 and N 2 The volume ratio of (3) is 55 percent, the recrystallization annealing is carried out at 1010 ℃ under 45 percent atmosphere, the annealing time is 6min, the rapid cooling is carried out at the speed of 60 ℃/s, and the coating is coated and coiled; and (3) carrying out aging treatment on the obtained annealed coil in a bell-type furnace, wherein the aging temperature is 400 ℃, the aging time is 80min, and then cooling to room temperature.
The magnetic property of the electrical steel is measured by using an Epstein square ring and the mechanical property is measured by using a tensile test method of a national standard GB/T228.1 metal material by using GB/T3655, the high-frequency iron loss P1.0/800 of the obtained product is 27.6W/kg, the magnetic induction B5000 is 1.68T, the yield strength Rp0.2 is 660Mpa, and the elongation is 6%.
Example 2:
elemental composition of the non-oriented silicon steel strip of this embodiment: 0.001wt% of C, 0.0008wt% of S, 0.002wt% of N, 0.0005wt% of Ti, 3.5wt% of Si, 0.8wt% of Al, 0.2wt% of Mn, 0.8wt% of Cu, 0.01wt% of P, 0.002wt% of V and 0.0015wt% of Zr, wherein the content of C+S+N+Ti is less than or equal to 80ppm; the balance of Fe and unavoidable impurities.
The manufacturing method of the non-oriented silicon steel thin strip in the embodiment comprises the following steps:
smelting, RH vacuum treatment and casting according to the above components, heating a casting blank to 1180 ℃, preserving heat for 1h, and rapidly hot-rolling to a hot-rolled coil with the thickness of 1.6 mm; normalizing the hot rolled coil in a pure nitrogen protective atmosphere, maintaining the normalizing temperature at 950 ℃ and the speed at 15m/min, and then rapidly cooling to room temperature; the two times of cold rolling of the normalizing plate adopt medium temperature rolling, the temperature is 450 ℃, the primary cold rolling reduction is 63%, the intermediate annealing temperature is 940 ℃, and the secondary cold rolling is carried out to obtain a cold-rolled coil with the thickness of 0.27 mm; h 2 And N 2 The volume ratio of (3) is 60 percent, the recrystallization annealing is carried out at 980 ℃ under the atmosphere of 40 percent, the annealing time is 8min, the rapid cooling is carried out at the speed of 55 ℃/s, and the coating is coated and coiled; and (3) carrying out aging treatment on the obtained annealed coil in a bell-type furnace, wherein the aging temperature is 350 ℃, the aging time is 45min, and then cooling to room temperature.
The magnetic property of the electrical steel is measured by using an Epstein square ring and the mechanical property is measured by using a national standard GB/T228.1 metal material tensile test method, the high-frequency iron loss P1.0/800 of the obtained product is 35.5W/kg, the magnetic induction B5000 is 1.67T, the yield strength Rp0.2 is 590Mpa, and the elongation is 8%.
Example 3:
elemental composition of the non-oriented silicon steel strip of this embodiment: 0.001wt% of C, 0.0005wt% of S, 0.0008wt% of N, 0.0005wt% of Ti, 3.4wt% of Si, 0.95wt% of Al, 0.25wt% of Mn, 1.6wt% of Cu, 0.01wt% of P, 0.0025wt% of V and 0.0015wt% of Zr, wherein the content of C+S+N+Ti is less than or equal to 50ppm; the balance of Fe and unavoidable impurities.
The manufacturing method of the non-oriented silicon steel thin strip in the embodiment comprises the following steps:
smelting, RH vacuum treatment and casting according to the above components, heating a casting blank to 1150 ℃, preserving heat for 1h, and rapidly hot-rolling to a hot-rolled coil with the thickness of 2.0 mm; normalizing and pickling the hot rolled coil in a pure nitrogen protective atmosphere, maintaining the normalizing temperature at 1030 ℃ and the speed at 20m/min, and then rapidly cooling to room temperature; the two times of cold rolling of the normalizing plate adopt medium temperature rolling, the temperature is 450 ℃, the primary cold rolling reduction is 73%, the intermediate annealing temperature is 970 ℃, and the secondary cold rolling is carried out to obtain a cold-rolled coil with the thickness of 0.25 mm; h 2 And N 2 The volume ratio of (2) is 65 percent, the recrystallization annealing is carried out at 1050 ℃ under 35 percent atmosphere, the annealing time is 4min, the rapid cooling is carried out at the speed of 55 ℃/s, and the coating is coated and coiled; and (3) carrying out aging treatment on the obtained annealed coil in a bell-type furnace, wherein the aging temperature is 450 ℃, the aging time is 130min, and then cooling to room temperature.
The magnetic property of the electrical steel is measured by using an Epstein square ring and the mechanical property is measured by using a national standard GB/T228.1 metal material tensile test method, the high-frequency iron loss P1.0/800 of the obtained product is 33.1W/kg, the magnetic induction B5000 is 1.69T, the yield strength Rp0.2 is 720Mpa, and the elongation is 4%.
Example 4:
elemental composition of the non-oriented silicon steel strip of this embodiment: 0.0025wt% of C, 0.001wt% of S, 0.0005wt% of N, 0.001wt% of Ti, 3.1wt% of Si, 1wt% of Al, 0.45wt% of Mn, 1.2wt% of Cu, 0.0085wt% of P, 0.002wt% of V and 0.001wt% of Zr, wherein the content of C+S+N+Ti is less than or equal to 80ppm; the balance of Fe and unavoidable impurities;
the manufacturing method of the non-oriented silicon steel thin strip in the embodiment comprises the following steps:
smelting and RH vacuum treatment and casting according to the above componentsAfter casting, heating the casting blank to 1100 ℃, preserving heat for 1h, and rapidly hot-rolling to a hot-rolled coil with the thickness of 1.8 mm; normalizing and pickling the hot rolled coil in a pure nitrogen protective atmosphere, maintaining the normalizing temperature at 1010 ℃ and the speed at 20m/min, and then rapidly quenching the hot rolled coil to room temperature; the two times of cold rolling of the normalizing plate adopt medium temperature rolling, the temperature is 400 ℃, the primary cold rolling reduction is 65%, the intermediate annealing temperature is 920 ℃, and the secondary cold rolling is carried out to obtain a cold-rolled coil with the thickness of 0.30 mm; h 2 And N 2 The volume ratio of (3) is 60 percent, the recrystallization annealing is carried out at 1000 ℃ under the atmosphere of 40 percent, the annealing time is 6min, the rapid cooling is carried out at the speed of 60 ℃/s, and the coating is coated and coiled; and (3) carrying out aging treatment on the obtained annealed coil in a bell-type furnace, wherein the aging temperature is 400 ℃, the aging time is 80min, and then cooling to room temperature.
The magnetic property of the electrical steel is measured by using an Epstein square ring and the mechanical property is measured by using a national standard GB/T228.1 metal material tensile test method, the high-frequency iron loss P1.0/800 of the obtained product is 38.6W/kg, the magnetic induction B5000 is 1.71T, the yield strength Rp0.2 is 620Mpa, and the elongation is 7%.
The foregoing examples are illustrative of the present invention and are not intended to be limiting, and any other substitutions, modifications, combinations, alterations, simplifications, etc. which do not depart from the spirit and principles of the present invention are intended to be within the scope of the present invention.
Claims (9)
1. The non-oriented silicon steel is characterized by comprising the following components in percentage by weight: 0.001-0.003 wt% of C, less than or equal to 0.001wt% of S, less than or equal to 0.003wt% of N, less than or equal to 0.001wt% of Ti, 3.1-3.5 wt% of Si, 0.7-1.3 wt% of Al, 0.1-1.0 wt% of Mn, 0.8-1.7 wt% of Cu, less than or equal to 0.02wt% of P, 0.0015-0.003wt% of V, 0.001-0.002 wt% of Zr, and the balance of Fe and unavoidable impurities;
the manufacturing method of the non-oriented silicon steel comprises the following steps: (1) Carrying out normalizing acid washing treatment on the hot rolled coil to obtain a normalizing coil; (2) Performing warm rolling on the normalized coil by adopting a twice cold rolling method to obtain a cold-rolled coil; (3) The cold rolled coil is subjected to recrystallization annealing and cooling to obtain an annealed coil; (4) aging and cooling the annealed coil; in the step (2), the rolling temperature is 300-450 ℃, the rolling reduction of the first cold rolling is 60-75%, then the intermediate annealing is carried out at 850-1000 ℃, and then the second cold rolling is carried out, wherein the rolling reduction is 40-65%.
2. The non-oriented silicon steel according to claim 1, wherein the composition, in weight percentage, is: 0.001-0.003 wt% of C, less than or equal to 0.001wt% of S, less than or equal to 0.003wt% of N, less than or equal to 0.001wt% of Ti, 3.3-3.5 wt% of Si, 0.8-1.0 wt% of Al, 0.2-0.5 wt% of Mn, 0.8-1.7 wt% of Cu, 0.005-0.015 wt% of P, 0.0015-0.002 wt% of V, 0.001-0.0015 wt% of Zr, and the balance of Fe and unavoidable impurities.
3. The non-oriented silicon steel according to claim 1, wherein the sum of the contents of C, S, N and Ti satisfies c+s+n+ti to 80ppm or less.
4. The non-oriented silicon steel as claimed in claim 3, wherein the sum of the contents of C, S, N and Ti satisfies C+S+N+Ti to be less than or equal to 50ppm.
5. The non-oriented silicon steel according to any one of claims 1 to 4, wherein the high frequency core loss P1.0/800 of the non-oriented silicon steel is 27 to 39w/kg, the magnetic induction B5000 is 1.67 to 1.72t, and the yield strength rp0.2 is 560 to 720mpa.
6. The method for producing non-oriented silicon steel as claimed in any one of claims 1 to 5, comprising:
(1) Carrying out normalizing acid washing treatment on the hot rolled coil to obtain a normalizing coil;
(2) Performing warm rolling on the normalized coil by adopting a twice cold rolling method to obtain a cold-rolled coil;
(3) The cold rolled coil is subjected to recrystallization annealing and cooling to obtain an annealed coil;
(4) The annealed coil is aged and cooled.
7. The method according to claim 6, wherein in the step (1), the hot rolled coil is subjected to a normalizing pickling treatment under a protective atmosphere condition at a normalizing temperature of 950 to 1050 ℃ and a normalizing speed of 20m/min or less.
8. The method according to claim 6, wherein in the step (3), the recrystallization annealing is performed at H 2 And N 2 The process is carried out in an atmosphere with the volume ratio of more than 1:1, the temperature of recrystallization annealing is 900-1050 ℃, and the time of recrystallization annealing is 3-10 min.
9. The method according to claim 6, wherein in the step (4), the annealed roll is subjected to an aging treatment in a bell-type furnace at a temperature of 300 ℃ to 500 ℃ for 30min to 150min.
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