CN107964631B - Non-oriented silicon steel with yield strength of more than or equal to 500MPa for high-speed motor rotor and production method - Google Patents
Non-oriented silicon steel with yield strength of more than or equal to 500MPa for high-speed motor rotor and production method Download PDFInfo
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Abstract
The non-oriented silicon steel for the high-speed motor rotor with yield strength of more than or equal to 500MPa comprises the following chemical components in percentage by weight: si: 2.5-4.5%, Al: 0.8-2.0%, Mn: 0.5 to 2.0 percent, less than or equal to 0.005 percent of N, less than or equal to 0.002 percent of S, less than or equal to 0.003 percent of C, less than or equal to 0.05 percent of P, less than or equal to 0.05 percent of Cu, and less than or equal to 0.01 percent of Ti + Nb + V + Zr; the production method comprises the following steps: smelting in a converter and then carrying out RH vacuum refining; heating a casting blank; finish rolling after rough rolling; coiling; acid washing; cold rolling; and (6) annealing. Compared with the prior art, the invention can effectively improve the mechanical strength of the non-oriented silicon steel under the conditions of not adding additional alloy elements and omitting a normalizing process, the yield strength is not lower than 500MPa, and the iron loss of a finished product with the thickness of 0.35mm or less is P1.0/400≤18W/kg。
Description
Technical Field
The invention relates to non-oriented silicon steel and a production method thereof, in particular to non-oriented silicon steel with yield strength of more than or equal to 500MPa for a high-speed motor rotor and a production method thereof.
Background
The high-speed motor generally refers to a motor with the rotating speed of more than 10000r/min, has high power density and small volume, and has good application prospect in the fields of new energy automobiles, aviation and ships. Particularly, the high-speed permanent magnet synchronous motor has wide application in the field of new energy automobiles due to high power density, small size, light weight and wide rotating speed range. The width of a magnetic bridge in a permanent magnet synchronous motor rotor is narrow, and researches show that the narrower the width of the magnetic bridge is, the higher the permanent magnet torque and the total torque are, and the higher the motor efficiency is. The rotor is subjected to larger centrifugal stress in high-speed rotation, the stress is more concentrated due to the reduction of the width of the magnetic bridge, the rotor is easy to generate fatigue fracture in the frequent variable-speed rotation process, and the permanent magnet is embedded in the rotor. Therefore, the electrical steel sheet has high yield strength and high fatigue resistance to resist centrifugal force in consideration of safety requirements of the motor. In consideration of safety, it is considered that the yield strength of the non-oriented silicon steel sheet is preferably 500MPa or more through experimental studies.
Another index of the non-oriented electrical steel sheet for a rotor is iron loss. The magnetic field fluctuation component in the motor is mainly concentrated on the stator core, and the iron loss is mainly generated by the stator core, particularly stator teeth. The flux density variation is small in the rotor core and the permanent magnets, and large in the stator core. Losses in the rotor and permanent magnets are negligible with respect to stator core losses. And it can be expected from harmonic analysis that the harmonic component in the rotor has a small amplitude, and the iron loss in the stator is much larger than that of the rotor. Therefore, the loss generated in the rotor does not greatly affect the efficiency of the motor, and the iron loss of the non-oriented electrical steel sheet for the rotor is acceptable to be slightly higher than that of the material used for the stator. However, when the rotor is damaged, heat generated by the rotor has a demagnetization effect on the permanent magnet, the performance of the motor is indirectly deteriorated, the heat dissipation of the rotor core is more difficult compared with that of the stator core, the working temperature of the motor is increased due to high iron loss of the rotor, and the service life of a bearing and other electronic components is adversely affected. Therefore, the iron loss, particularly the high frequency loss, of the non-oriented silicon steel sheet for a rotor cannot be excessively high.
In order to inhibit fatigue deformation of the magnetic bridges under high-speed centrifugal force, the width of the magnetic bridges is difficult to be infinitely reduced, in addition, because the magnetic resistance of the silicon steel sheets is far lower than that of air, air gap magnetic flux in an iron core tends to penetrate through the magnetic bridges, thereby inevitably causing magnetic leakage and reducing the utilization rate of permanent magnets, but on the other hand, the torque of the permanent magnet synchronous motor also fully utilizes the magnetic resistance torque of a rotor, so that the non-oriented electrical steel plate for the rotor generally has no special requirements on magnetic induction.
Therefore, the non-oriented silicon steel electrical steel sheet for high-speed motor rotor must have high strength, and the iron loss level can be relatively loose, but not too high.
Referring to related patent documents at home and abroad, the methods for improving the mechanical strength of non-oriented silicon steel can be divided into two categories: namely precipitation strengthening and solid solution strengthening.
Document JP 2011-: c is less than or equal to 0.02 percent, Si is 1.6-3.0 percent, Mn is less than or equal to 1.0 percent, Al is 0.1-3.0 percent, Ni is less than or equal to 2.0 percent, Cu is 1.0-3.0 percent, and the solid solution precipitation of Ni and the precipitation strengthening action of Cu are comprehensively applied to improve the mechanical strength.
Document JP 2016-: c is less than or equal to 0.01 percent, Si is 0.2-4.0 percent, Mn is 0.05-2.0 percent, Al is less than or equal to 2.5 percent, Cu is 0.5-3.0 percent, and the precipitate of Cu is utilized for strengthening by annealing at 400-700 ℃ for more than 1s and less than 10 min.
Document JP 2013-44009A proposes a method for manufacturing non-oriented silicon steel for a rotor, which has the following composition characteristics: c is less than or equal to 0.01 percent, Si is 1.0-3.0 percent, Mn is 0.05-2.0 percent, Al is 0.1-2.0 percent, S + As + Nb + Ti + V + Zr + N is less than or equal to 0.018 percent, and carbon and nitrogen precipitates of the elements of Ti, Nb, V and Zr strongly inhibit the recrystallization process of the silicon steel, thereby achieving the purposes of refining grains and improving mechanical strength.
By performing the solid solution strengthening by increasing the contents of Si and Ni, the alloy cost is significantly increased although the finished product magnetic properties are not deteriorated, and the strength before rolling is increased by the solid solution strengthening, so that the rolling difficulty is increased.
When Cu is used for precipitation strengthening, the precipitation strengthening effect of Cu is very limited when the Cu content is less than 1%, the aging hardening amount is increased due to the increase of the Cu content, precipitates are unevenly dispersed and precipitated when a finished product is annealed when the Cu content exceeds 3%, the strength is reduced after aging heat treatment, and the magnetic flux density is reduced. Too high a Cu content also causes surface defects of the steel sheet and brittle fracture of the steel sheet at the time of cold rolling.
When the content of C exceeds 0.01%, the magnetic aging is remarkable, and precipitates are easily precipitated in large size. When the temperature of the non-oriented silicon steel reaches 200 ℃, carbide is formed, the iron loss is easily deteriorated, and the precipitates of Ti, Nb, V, and Zr strongly inhibit recrystallization, resulting in severe deterioration of the iron loss.
Therefore, how to reduce the alloy and production cost of the non-oriented silicon steel, obtain higher mechanical strength and ensure certain iron loss becomes a problem to be solved urgently in the prior non-oriented silicon steel for the rotor.
Disclosure of Invention
The invention aims to overcome the defects in the prior art and provide a steel plate with the thickness of 0.35mm or less, the yield strength of more than 500MPa, the iron loss P1.0/400Non-oriented silicon steel for high-speed motor rotor less than or equal to 18W/kg and a production method thereof.
The measures for realizing the aim are as follows:
the non-oriented silicon steel with yield strength more than or equal to 500MPa for the high-speed motor rotor comprises the following chemical components in percentage by weight: si: 2.5-4.5%, Al: 0.8-2.0%, Mn: 0.5-2.0 percent of N, less than or equal to 0.005 percent of S, less than or equal to 0.002 percent of S, less than or equal to 0.003 percent of C, less than or equal to 0.05 percent of P, less than or equal to 0.05 percent of Cu, less than or equal to 0.01 percent of Ti, Nb, V and Zr, and the balance of Fe and inevitable impurities.
Preferably: the weight percentage content of Si is 3.0-4.0%.
Preferably: the Al accounts for 1.0-1.6% of the total weight of the alloy.
Preferably: the Mn content is 8-1.5 wt%.
The method for producing the non-oriented silicon steel with yield strength of more than or equal to 500MPa for the high-speed motor rotor comprises the following steps:
1) carrying out RH vacuum refining after smelting in a converter;
2) heating the casting blank after continuous casting and forming, wherein the heating temperature is 1000-1200 ℃, and the heating time is not less than 100 min;
3) carrying out finish rolling after conventional rough rolling, and controlling the finish rolling temperature to meet the following requirements:
the finishing temperature is more than or equal to 650 ℃ and less than or equal to [650+ (Si + Al) x 50] ° C;
in the formula: si and Al are set weight percentage contents in the steel plate and are calculated according to the weight percentage data;
4) coiling at 500-600 ℃;
5) carrying out conventional acid washing;
6) performing cold rolling, and rolling to the thickness of a finished product not more than 0.35mm by adopting a one-time cold rolling method;
7) and annealing, namely heating to an annealing temperature under the condition that the heating speed is 40-100 ℃/s, wherein the annealing temperature is 600-700 ℃, and the heat preservation time is 1.5-3 min.
Preferably: the heating temperature of the casting blank is 1025-1150 ℃.
Preferably: the finish rolling temperature is equal to or higher than 750 ℃ and equal to or lower than 815 ℃;
preferably: the annealing heating speed in the step 7) is 50-88 ℃/s.
Effect of elements of the invention
(1)C:≤0.003%
C causes magnetic aging and also forms TiC to deteriorate the magnetic properties, so that the content thereof is reduced as much as possible.
(2)Si:2.5～4.5%
Since Si is an element for increasing the resistivity of the steel sheet to reduce the iron loss, the Si content needs to be more than 2.5%, and when the amount of Si added is too large, the steel sheet is embrittled to cause difficulty in rolling, so that the upper limit of the Si content is set to 4.5%. Further preferably, the Si content is 3.0 to 4.0%.
(3) Al:0.8～2.0%
The solid-dissolved aluminum can significantly reduce eddy current loss of steel by increasing the resistivity of ferrite, and can significantly reduce the total loss when the high-frequency eddy current loss ratio is large, so the Al content needs to be more than 0.5%, but Al significantly reduces the saturation magnetic induction Bs, has a large effect on embrittlement of the steel sheet, and is likely to cause internal oxidation during annealing, so the upper limit of the Al content is set to 2.0%. Further preferably, the Al content is 1.0 to 1.6%.
(4)Mn:0.5～2.0%
Mn can improve hot rolling plasticity, increase the hardness of the steel plate and improve the punching property of the steel plate, and when Mn is less than or equal to 0.5%, the iron loss can not be fully reduced, and the iron loss of fine precipitates is increased. When Mn is 2.0% or more, a large amount of Mn carbide is formed, resulting in an increase in iron loss. More preferably, the Mn content is 0.8 to 1.5%.
(5) S:≤0.002%
S causes the precipitation of MnS, TiS and CuS, thus inhibiting the growth of crystal grains and deteriorating the magnetism.
(6)N:≤0.003%
N is contained in an amount of 0.003% or less because it causes precipitation of AlN or TiN and inhibits grain growth during annealing.
(7)P:0.005～0.05%
P is set to 0.005% or more because it can increase the resistivity, increase the strength of the steel sheet, and improve the punching properties. However, if the P content exceeds 0.05%, the steel sheet becomes brittle and the production risk increases.
(8)Cu:≤0.05%
Cu is not an essential element, and fine sulfide is formed to deteriorate the magnetic property, so that the lower the Cu content, the better.
(9)Ti+Nb+V+Zr:≤0.01%
Ti, Nb, V and Zr are carbide and nitride forming elements, and precipitates of Ti, Nb, V and Zr can effectively inhibit recrystallization of a steel plate, improve dislocation density and refine crystal grains, so that the strength of the steel plate is improved. Therefore, Ti + Nb + V + Zr is limited to 0.01% or less, preferably 0.005% or less.
Next, the operation of the texture of the present invention will be described.
The <111> direction of the iron single crystal of the body-centered cubic system is the atomic packing direction, the elastic modulus (strength) is the largest and 248GPa, while the atomic density in the <100> direction is the smallest and the elastic modulus is the smallest and 165GPa, and the elastic modulus of the main crystal direction is shown in FIG. 1.
From the viewpoint of improving strength, it is desirable that the crystal plane of the material contains as much as possible the crystal orientation of <111> or the like, and does not contain the crystal orientation of <100> or the like. For example, the {211}, {321}, {431}, {110} crystal planes all contain the <111> crystal orientation, but the {110} crystal plane contains the <001> crystal orientation. Therefore, it is finally desired to improve the strength of the {211}, {321}, {431} crystal plane components to improve the mechanical properties of the finished product. And the {100} plane texture contains crystal orientations of <001>, <010>, <310>, <210> and the like, so that the component strength is reduced as much as possible.
The silicon steel production processes all have influence on the texture of a finished product, for example, with the increase of the finishing rolling temperature, the recrystallization after hot rolling is easier, the recrystallization rate is higher, the {100} surface texture of a hot rolled plate is enhanced, and the {110} and {111} surface texture strength is weakened. Normalization after hot rolling can make the hot rolled plate structure more uniform, increase the recrystallized grains, strengthen the {100} and {110} components, and weaken the {111}, {211}, {321}, and {431} plane texture. In order to better optimize the composition of the texture and thus increase the mechanical strength, the texture enhancing factor Is defined here
The larger the value of Is, the greater the contribution to the mechanical strength, and the higher the mechanical strength of the material. Considering that the texture also has a certain influence on the magnetic properties of the finished product, the texture such as {211}, {321}, {431} Is disadvantageous to the iron loss, and the texture such as {100}, {110} Is advantageous to the iron loss, so that the adverse effect on the iron loss Is more serious as the value of Is larger.
Comprehensively considering the influence of the texture strengthening factor Is on the mechanical strength and magnetism, the range of Is regulated to be 1.0-2.0, and the preferable range of Is 1.3-1.8.
Effect of the Main Process in the invention
(1) As the finishing temperature of hot rolling is increased, recrystallization after hot rolling becomes easier, the recrystallization rate becomes higher, the {100} plane texture of the hot-rolled sheet is enhanced, and the {110} and {111} plane texture strengths are weakened. The final rolling temperature is too low, crystal grains are too fine, if the crystal grains are not normalized, the rolling load is too large during cold rolling, a steel plate is easy to break, the final rolling temperature is too high, the crystal grains are too coarse, the {100} surface texture is enhanced, and the {100} surface texture of a finished product after annealing is too strong and the strength of the finished product is reduced due to the inheritance of the texture. Therefore, the hot rolling finishing temperature range is defined as: the finishing temperature is 650 ℃ or more and [650+ (Si + Al) x 50] DEG C or less, and the finishing temperature is more preferably: 750 and 815 ℃.
(2) When the hot rolling coiling temperature is lower than 500 ℃, the upper surface and the lower surface of the sample are recrystallized structures, the middle part lacks recrystallization driving force, the recrystallized structures are not generated, solute atoms are difficult to effectively diffuse for a long distance in a short time, precipitates such as AlN are easily formed dispersedly, grain boundaries are pinned after cold rolling annealing, and the iron loss of the finished product after annealing is deteriorated. When the coiling temperature is higher than 600 ℃, the microstructure is grown after static recrystallization, and simultaneously, the dissolution of fine precipitates and the diffusion of solute atoms are included, the central recrystallized structure is increased, the fiber band is reduced, the textures such as {111}, {211}, {321}, {431} and the like are reduced, and the inheritability of the textures leads to the weakening of the textures of {211}, {321}, and {431} surfaces after annealing, so that the strength of the finished product is reduced. Therefore, the hot rolling coiling temperature range is defined as: 500 ℃ and 600 ℃.
(3) The normalization process is omitted after hot rolling because the normalization after hot rolling can make the texture of the hot rolled plate more uniform, increase the recrystallized grains, strengthen the {100} and {110} components, and weaken the {111}, {211}, {321}, and {431} surface texture. Considering that the inheritance of the texture can cause that the {100} plane texture of the finished product after annealing is too strong, the {211}, {321}, and {431} plane texture is weakened, and the strength of the finished product is reduced.
(4) Annealing of a finished product: the heating speed is less than or equal to 40 ℃/s and less than or equal to 100 ℃/s. The annealing heating speed has a great relationship with the texture of the finished product, under the condition of high heating speed, the composition of the Gaussian texture {110} <001> in the hot rolling initial coarse grain sample is obviously enhanced, the texture of {111}, {211}, {321}, and {431} is slightly weakened, and the strength of the Gaussian texture in the hot rolling initial fine grain sample is reduced, but the texture of {111}, {211}, {321}, and {431} is greatly reduced. Under the condition of low heating rate, the weaker {110} component in the hot-rolled initial coarse grain sample becomes stronger, while the strength of the Gaussian texture component in the finished product corresponding to the hot-rolled initial fine grain sample is reduced, and the strength of the {111}, {211}, {321}, {431} and other texture components is greatly improved. The reason is that the nucleation of the gaussian oriented grains generally occurs early in the annealing with more chance of growing up, but the recovery occurring under the condition of low heating rate is stronger, and the difference of the residual energy storage between the texture components before the recrystallization starts is weakened, so that the chance of growing up the gaussian grains is reduced, and at the same time, the main texture components {111}, {211}, {321}, and {431} crystal nucleus components at the early stage of recrystallization grow up by consuming the surrounding deformed matrix. In the invention, when the hot rolling finishing temperature is lower and the normalizing process is cancelled, the crystal grains of the hot rolled plate are smaller, when the annealing heating speed is more than 100 ℃/s, the strength of the Gaussian texture in the finished product corresponding to the initial fine-grain sample in hot rolling is improved, the strength of texture components such as {111}, {211}, {321}, {431} and the like is greatly reduced, which is not beneficial to improving the strength of the finished product, but when the annealing heating speed is less than 40 ℃/s, the strength of the Gaussian texture is weakened, {111}, {211}, {321}, {431} and the like are greatly improved, which can cause the iron loss to be greatly reduced, therefore, after the hot rolling finishing temperature is met and the normalizing process is cancelled, the annealing heating speed of the finished product is controlled to be 40-100 ℃/s, and the: 50-88 ℃/s.
Compared with the prior art, the invention can effectively improve the mechanical strength of the non-oriented silicon steel under the conditions of not adding additional alloy elements and omitting a normalizing process, the yield strength is more than 500MPa, and the iron loss of a finished product with the thickness of 0.35mm or less is P1.0/400≤18W/kg。
Drawings
FIG. 1 is a schematic diagram showing the elastic modulus of the main crystal orientation in the body-centered cubic system of the present invention.
Detailed Description
The present invention is described in detail below:
the embodiments of the invention are produced according to the following steps:
1) carrying out RH vacuum refining after smelting in a converter;
2) heating the casting blank after continuous casting and forming, wherein the heating temperature is 1000-1200 ℃, and the heating time is not less than 100 min;
3) carrying out finish rolling after conventional rough rolling, and controlling the finish rolling temperature to meet the following requirements:
the finishing temperature is more than or equal to 600 ℃ and less than or equal to [650+ (Si + Al) x 50] ° C;
in the formula: si and Al are set weight percentage contents in the steel plate and are calculated according to the weight percentage data;
4) coiling at 500-600 ℃;
5) carrying out conventional acid washing;
6) performing cold rolling, and rolling to a finished product thickness of 0.35mm or less by adopting a one-time cold rolling method;
7) annealing, heating to an annealing temperature of 600-700 ℃ at a heating speed of 40-100 ℃/s.
Examples
Smelting in a converter, wherein the specific components of the test steel are shown in table 1, carrying out RH vacuum treatment, and continuously casting to form a blank. Heating the casting blank, then carrying out rough rolling, finish rolling, coiling, normalizing after hot rolling or directly carrying out acid pickling, and carrying out primary cold rolling to 0.35mm after acid pickling. And (3) annealing the cold-rolled sheet to obtain a finished product, wherein the specific process is shown in Table 2. The corresponding texture strengthening factor and performance of the finished product are shown in Table 3.
TABLE 1 tabulated values (wt%) for inventive and comparative examples
TABLE 2 corresponding Process List for each composition example of the present invention
TABLE 3 table of properties corresponding to each composition example of the present invention
As can be seen from the above examples, only when the chemical composition meets the claims, the hot rolling finishing temperature is more than or equal to 600 ℃ and less than or equal to [650+ (Si + Al) x 50] DEG C, the coiling temperature is 600 ℃ plus 500 ℃, the normalizing process is not adopted, the annealing heating speed is 40-100 ℃/s, the annealing temperature is 600 ℃ plus 700 ℃, the soaking time is 1.5-3min, the texture strengthening factor of the material reaches the target, and the mechanical property and the iron loss of the material can meet the target requirements at the same time. And by adopting the preferable components and processes, the mechanical property and the iron loss of the material are more excellent.
The above examples are merely preferred examples and are not intended to limit the embodiments of the present invention.
Claims (3)
1. The method for producing the non-oriented silicon steel with yield strength of more than or equal to 500MPa for the high-speed motor rotor comprises the following steps:
the non-oriented silicon steel for the high-speed motor rotor with the yield strength of more than or equal to 500MPa comprises the following chemical components in percentage by weight: si: 4.12-4.5%, Al: 1.62-2.0%, Mn: 0.5-2.0 percent of N, less than or equal to 0.005 percent of S, less than or equal to 0.002 percent of S, less than or equal to 0.003 percent of C, less than or equal to 0.05 percent of P, less than or equal to 0.05 percent of Cu, less than or equal to 0.01 percent of Ti + Nb + V + Zr, and the balance of impurities which are not prevented by Fe;
1) carrying out RH vacuum refining after smelting in a converter;
2) heating the casting blank after continuous casting and forming, wherein the heating temperature is 1000-1078 ℃ or 1168-1200 ℃, and the heating time is not less than 100 min;
3) carrying out finish rolling after conventional rough rolling, and controlling the finish rolling temperature to meet the following requirements:
the finishing temperature is more than or equal to 650 ℃ and less than or equal to [650+ (Si + Al) x 50] ° C;
in the formula: si and Al are set weight percentage contents in the steel plate and are calculated according to the weight percentage data;
4) coiling at 500-600 ℃;
5) carrying out conventional acid washing;
6) performing cold rolling, and rolling to the thickness of a finished product which is not more than 0.35mm by adopting a one-time cold rolling method;
7) and annealing, namely heating to an annealing temperature under the condition that the heating speed is 40-100 ℃/s, wherein the annealing temperature is 600-700 ℃, and the heat preservation time is 1.5-2.9 min.
2. The method for producing the non-oriented silicon steel with yield strength of more than or equal to 500MPa for the high-speed motor rotor as claimed in claim 1 is characterized in that: the finish rolling temperature in the step 3) is more than or equal to 750 ℃ and less than or equal to 815 ℃.
3. The method for producing the non-oriented silicon steel with yield strength of more than or equal to 500MPa for the high-speed motor rotor as claimed in claim 1 is characterized in that: the annealing heating speed in the step 7) is 50-88 ℃/s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711352947.9A CN107964631B (en) | 2017-12-15 | 2017-12-15 | Non-oriented silicon steel with yield strength of more than or equal to 500MPa for high-speed motor rotor and production method |
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| CN110172560B (en) * | 2019-05-30 | 2020-07-03 | 江苏良工精密合金钢有限公司 | Preparation method of high-Si-content electrical steel |
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| CN115323283B (en) * | 2022-08-18 | 2023-08-11 | 山西太钢不锈钢股份有限公司 | Low-alloy high-strength non-oriented silicon steel and production method thereof |
| CN115198199A (en) * | 2022-09-14 | 2022-10-18 | 张家港扬子江冷轧板有限公司 | Production method of high-strength non-oriented silicon steel, high-strength non-oriented silicon steel and application |
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