CN116426810A - Preparation method of high-frequency low-iron-loss non-oriented silicon steel for new energy automobile driving motor - Google Patents
Preparation method of high-frequency low-iron-loss non-oriented silicon steel for new energy automobile driving motor Download PDFInfo
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- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 52
- 238000002360 preparation method Methods 0.000 title description 3
- 238000000137 annealing Methods 0.000 claims abstract description 85
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 68
- 238000000034 method Methods 0.000 claims abstract description 41
- 238000001953 recrystallisation Methods 0.000 claims abstract description 39
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 38
- 239000010959 steel Substances 0.000 claims abstract description 38
- 238000002791 soaking Methods 0.000 claims abstract description 35
- 229910052742 iron Inorganic materials 0.000 claims abstract description 32
- 230000008569 process Effects 0.000 claims abstract description 29
- 238000001816 cooling Methods 0.000 claims abstract description 25
- 238000004519 manufacturing process Methods 0.000 claims abstract description 20
- 238000003723 Smelting Methods 0.000 claims abstract description 16
- 238000005097 cold rolling Methods 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 12
- 238000005266 casting Methods 0.000 claims abstract description 11
- 230000001590 oxidative effect Effects 0.000 claims abstract description 11
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 7
- 239000000956 alloy Substances 0.000 claims abstract description 7
- 239000011248 coating agent Substances 0.000 claims abstract description 7
- 238000000576 coating method Methods 0.000 claims abstract description 7
- 238000005098 hot rolling Methods 0.000 claims abstract description 6
- 230000000630 rising effect Effects 0.000 claims description 6
- 229910052717 sulfur Inorganic materials 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims description 4
- 239000000463 material Substances 0.000 abstract description 9
- 239000000203 mixture Substances 0.000 abstract description 3
- 239000000047 product Substances 0.000 description 17
- 239000011572 manganese Substances 0.000 description 14
- 230000000052 comparative effect Effects 0.000 description 12
- 229910052710 silicon Inorganic materials 0.000 description 11
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 8
- 239000010703 silicon Substances 0.000 description 8
- 230000035882 stress Effects 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 230000005389 magnetism Effects 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000009628 steelmaking Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 241001391944 Commicarpus scandens Species 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 241001062472 Stokellia anisodon Species 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 125000004432 carbon atom Chemical group C* 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
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- 125000004433 nitrogen atom Chemical group N* 0.000 description 1
- 229910017464 nitrogen compound Inorganic materials 0.000 description 1
- 150000002830 nitrogen compounds Chemical class 0.000 description 1
- 238000010606 normalization Methods 0.000 description 1
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- 238000012545 processing Methods 0.000 description 1
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- 239000011593 sulfur Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000009466 transformation Effects 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
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- 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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- 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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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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Abstract
The invention discloses a manufacturing method of high-frequency low-iron-loss non-oriented silicon steel for a new energy automobile driving motor, which comprises the following steps of (1) smelting alloy and molten iron in a smelting furnace according to a proportion to obtain molten steel; (2) Smelting and continuously casting molten steel by a converter, and heating a casting blank to 1100-1220 ℃; (3) After conventional hot rolling to a hot rolled plate with the thickness of 2.0mm, carrying out normalizing annealing at 900-1200 ℃ for 100-240 s; (4) Then cold rolling is carried out to the thickness of a finished product, and a non-oriented silicon steel plate with the thickness of 0.25+/-0.005 mm is obtained; (5) finally performing recrystallization annealing; the annealing heating rate is 70-100 ℃/s; the annealing atmosphere of the soaking section in the recrystallization annealing process adopts a partial pressure ratio of P (H 2 O)/P(H 2 ) A non-oxidizing atmosphere of =0.0002 to 0.0005; (6) Cooling the mixture after recrystallization annealing at a cooling speed of 7-10 ℃/s; (8) Finally, an insulating coating is coated and dried at 300-550 ℃. The invention can control the recrystallization annealing process to prepare the non-oriented silicon steel material which can meet the requirements of high frequency and low iron loss of the non-oriented silicon steel material for the driving motor of the new energy automobile.
Description
Technical Field
The invention belongs to the field of steel product production, and particularly relates to a preparation method of high-frequency low-iron-loss non-oriented silicon steel for a driving motor of a new energy automobile.
Background
New energy automobiles are a necessary trend of future automobile development. The driving motor is a heart of the new energy automobile, the performance of the driving motor determines the main performance index of the automobile running, the duty ratio of the driving motor is the largest in the power consumption of the new energy automobile, and the high efficiency and energy conservation of the new energy automobile are determined. The non-oriented silicon steel is used as a core raw material of a driving motor, and the performance of the non-oriented silicon steel plays a decisive role in the future industrial development of new energy automobiles.
The maximum rotation speed of the driving motor of the new energy automobile is increased from thousands of revolutions per minute to tens of thousands of revolutions even up to 20 tens of thousands of revolutions, and the working frequency is increased from 50Hz to hundreds of thousands of Hz, so that the non-oriented silicon steel material is required to have low iron loss at high frequency. The iron loss is reduced when the motor does work, and the continuous voyage mileage of the vehicle is improved under the condition of using batteries with the same electric quantity. The iron loss of the traditional 0.5mm thick high-grade non-oriented silicon steel is less than 3.5W/kg under the conditions of magnetic flux density of 1.5T and frequency of 50Hz, but when the frequency is increased to 400Hz, the iron loss is more than 80W/kg. Therefore, the conventional high-grade non-oriented silicon steel can not meet the requirements of high frequency and low iron loss at present, and the production of the non-oriented silicon steel material for the driving motor of the new energy automobile is challenged.
Patent CN114196887A discloses a non-oriented silicon steel for a new energy driving motor and a production method thereof, cu, cr, ni, nb, V, ti is not added during steelmaking, 4.6% -4.9% of Si+2Al is satisfied, al/N is more than or equal to 200, the size of recrystallized grains is controlled to be 50-80 mu m, and the normalizing temperature is 840-860 ℃ and the temperature is kept for 180-200 s. The method mainly improves the performance of the non-oriented silicon steel through component design, and improves the strength of the non-oriented silicon steel, but the iron loss is still higher at 400Hz and exceeds 30W/kg, so that the requirement of high-frequency low iron loss of the non-oriented silicon steel for a new energy driving motor is not met.
The patent CN112322972A discloses a method for improving the comprehensive performance of high-strength non-oriented high-silicon steel by normalizing treatment, which only adopts silicon as a solid solution strengthening element, does not add other alloying elements, and maintains the temperature at 800-1200 ℃ for 0.5-60min and air-cools to ensure that the microstructure of a hot-rolled plate is entirely composed of coarse equiaxed crystals, and the grain size of the normalized hot-rolled plate is 100-1500 mu m. The method mainly improves the strength of the electrical steel by improving the content of silicon element and adopting the silicon element as a solid solution strengthening element and combining dislocation strengthening, and can effectively improve the resistivity of the steel and reduce the iron loss. However, the method has the defect that the obtained normalized hot rolled plate has overlarge grain size due to overhigh silicon element content, and is easy to break in the subsequent cold rolling process, thereby being unfavorable for the continuous production of non-oriented silicon steel.
Patent CN114606445a discloses a production method of unoriented silicon steel, and the chemical components of the continuous casting billet comprise the following components in percentage by mass: c is less than or equal to 0.003%, si:3.5-4.5%, al:0.8-1.2%, mn:0.25-0.80%, ni:0.5-0.98%, P is less than or equal to 0.02%, S is less than or equal to 0.0020%, N is less than or equal to 0.0020%, nb is less than or equal to 0.0020%, V is less than or equal to 0.0020%, ti is less than or equal to 0.0020%, and the balance is Fe and unavoidable impurities; the addition relation of Ni and Si/Al content is Ni=2 (Si-2.5)/5+ (Al-0.3)/5; the soaking temperature of the normalizing annealing is=850+120 x, and the soaking time is 120-150s; the normalizing annealing soaking temperature is in unit DEG C, x is the addition amount of Ni, and the average grain size after normalization is 90+/-20 mu m. The soaking temperature of the soaking section is 950-1050 ℃, and the soaking time is 50-70s; the temperature rising rate of the temperature rising section in the final annealing process is 30-40 ℃/s, and the unit tension of the temperature rising section and the soaking section is controlled to be 3.5-4.5N/mm 2 The cooling rate of the cooling section is less than or equal to 5 ℃/s; pure N is adopted in the annealing process 2 Protecting, and controlling dew point at-20- -30deg.C. The method aims at the non-oriented silicon steel product with high silicon content, improves the toughness of the high silicon steel material by adding micro-alloy element Ni, and obtains the non-oriented silicon steel product with high strength, which increases the steelmaking cost on one hand and increases the steelmaking cost on the other handThe strip breakage in the cold rolling process is easily caused by the excessively high surface Si content, the production difficulty of non-oriented silicon steel is increased, and the mass production of the non-oriented silicon steel for the new energy driving motor cannot be realized.
Patent CN110205462A discloses a production method of non-oriented silicon steel for high-speed motor, which comprises the steps of normalizing a hot rolled plate, pickling, cold-rolling to critical thickness, then recrystallising, annealing, cold-rolling to target finished product thickness by adopting critical reduction of X%, and coating to obtain iron loss P 1.0/400 Less than or equal to 30W/kg and yield strength R p0.2 Not less than 500MPa, hardness HV 5 A finished product A less than or equal to 280; 2) Removing the residual hot rolled plate after the finished product A in the step 1) and carrying out stress relief annealing to obtain the iron loss P 1.0/400 Less than or equal to 20W/kg and magnetic induction B 5000 And the finished product B is more than or equal to 1.64T. The invention avoids the production and processing problems caused by the addition of alloy elements, but adopts a secondary cold rolling process of intermediate annealing, thereby increasing the production cost, and the iron loss of the product under high frequency is still higher, and the iron loss needs to be further reduced by stress relief annealing.
CN112501407a discloses a non-oriented silicon steel plate for high-efficiency variable frequency compressor and a production method thereof, which adopts a clean steel smelting method to smelt and continuously cast into billets, wherein the content of casting billets is less than or equal to 2.8 percent (si+als+mn)% and less than or equal to 4.0 percent, and the content of (v+nb+ti+n+s+c)% is less than or equal to 0.012 percent; heating and preserving heat of the continuous casting billet, and then carrying out hot rolling and coiling; normalizing and preserving heat, and then cooling, wherein the cooling speed V meets the following conditions: v is less than or equal to 105× (V+Nb+Ti+N+S+C); after pickling, carrying out cold rolling for one time to a thickness of more than 0.25mm and more than 0.25 mm; adopting a continuous annealing furnace to carry out recrystallization annealing and heat preservation, wherein the tension F of the steel belt in the furnace meets the following conditions: f is more than or equal to 30 x (Si+Als+Mn)% -15 x d; and (5) coating to obtain the non-oriented silicon steel plate for the high-efficiency variable frequency compressor. The invention does not consider the influence of the recrystallization annealing temperature on the magnetism, and the magnetism of the product is easy to be unstable.
Disclosure of Invention
The invention aims to provide a manufacturing method of non-oriented silicon steel for a new energy automobile driving motor, which meets the requirements of high frequency and low iron loss of non-oriented silicon steel materials for the new energy automobile driving motor.
The technical scheme of the invention is as follows:
a manufacturing method of high-frequency low-iron-loss non-oriented silicon steel for a new energy automobile driving motor comprises the following steps:
(1) Smelting alloy and molten iron in a smelting furnace according to a proportion to obtain molten steel, wherein the molten steel comprises the following components in percentage by weight: c is less than or equal to 0.003 percent, si:2.8% -3.2%, al:1.0-1.5%, mn:0.15-0.35%, P:0.01-0.015%, S less than or equal to 0.0020%, N less than or equal to 0.0015%, V+Ti+Nb less than or equal to 0.0020%, and the balance of Fe and unavoidable impurities;
(2) Smelting and continuously casting molten steel by a converter, and heating a casting blank to 1100-1220 ℃;
(3) After conventional hot rolling to a hot rolled plate with the thickness of 2.0mm, carrying out normalizing annealing at 900-1200 ℃ for 100-240 s;
(4) Then cold rolling is carried out to the thickness of a finished product, and a non-oriented silicon steel plate with the thickness of 0.25+/-0.005 mm is obtained;
(5) Finally, carrying out recrystallization annealing; the recrystallization annealing treatment process comprises the steps of heating, soaking and cooling in the annealing process;
the temperature rising speed in the recrystallization annealing process is 70-100 ℃/s;
the annealing atmosphere of the soaking section in the recrystallization annealing process adopts a partial pressure ratio of P (H 2 O)/P(H 2 ) A non-oxidizing atmosphere of =0.0002 to 0.0005;
cooling after recrystallization annealing;
(6) Finally, an insulating coating is coated and dried at 300-550 ℃.
Wherein, the recrystallization annealing soaking temperature in the step (5) satisfies the following relation:
230×([Si]+[Al]-[Mn])-20≤T≤240×([Si]+[Al]-[Mn])(1)
wherein T is annealing soaking temperature in unit DEG C; [ Si ] is the addition amount of Si in units; [ Al ] is the addition amount of Al in units; mn is the amount of Mn added in unit%.
Wherein the soaking time of the recrystallization annealing process in the step (5) is 5-20s.
Wherein the partial pressure ratio of the non-oxidizing atmosphere of the soaking section annealing atmosphere in the step (5) is P (H) 2 O)/P(H 2 )＝0.0002-0.0005。
Wherein, the cooling in the step (5) is controlled at 7-10 ℃/s.
The molten steel suitable for the invention comprises the following components in percentage by weight: c is less than or equal to 0.003 percent, si:2.8% -3.2%, al:1.0-1.5%, mn:0.15-0.35%, P:0.01-0.03%, S less than or equal to 0.0020%, N less than or equal to 0.0015%, V+Ti+Nb less than or equal to 0.0020%, and the balance of Fe and unavoidable impurities.
C is less than or equal to 0.003 percent: the low carbon is favorable for reducing the solid solubility of AlN, coarse AlN in steel is not easy to be dissolved in solid, fine AlN can be prevented from being precipitated, the final annealing temperature is increased to promote the growth of crystal grains, the magnetism is improved, the upper limit of the C content is set to 0.003%, and the difficulty is increased when the C content is too low.
Si:2.8% -3.2%, silicon can effectively improve the resistivity of the steel plate and reduce the iron loss of the finished product. However, when the silicon content is increased, cold rolling property is lowered, and stable mass production is difficult.
Al:1.0-1.5%, the effect of aluminum on magnetic properties is similar to that of silicon, the resistivity of the steel plate is improved, crystal grains are grown, and the iron loss of a finished product is reduced. Aluminum increases the {100} component and decreases the {111} component, which is advantageous for improving the magnetic properties. Since fine AlN precipitates during cooling of the hot rolled sheet and prevents the growth of crystal grains to deteriorate the iron loss, the Al content is not excessively high, and the Al content is limited to 1.0 to 1.5% in the present invention.
N is less than or equal to 0.0015 percent: the N content is high, and the iron loss is increased. Therefore, the upper limit of the N content in the present invention is set to 0.0015%.
P:0.01-0.03%: the P element can be biased along the grain boundary, so that the brittleness of the silicon steel is increased, and the P content is reduced. But P is an effective element for ensuring grain growth by stress relief annealing, and the content of P is 0.01-0.03 percent.
S is less than or equal to 0.0020 percent: s content is reduced, and iron loss of silicon steel is reduced. Therefore, the upper limit of the S content in the present invention is set to 0.0020%.
Mn:0.25-0.35%: manganese and sulfur element in steel form fine MnS precipitate, mn can coarsen MnS, and grain growth is facilitated. The Si+Al content is increased, the bonding phenomenon is easy to generate when the sheet is punched, the sheet is deteriorated, mn can alleviate the phenomenon, and the sheet punching property and the cutting property are improved. The S content in the steel is reduced, and the Mn content is also reduced. The Mn content of the present invention is set to 0.25-0.35%.
Nb+V+Ti is less than or equal to 0.0020 percent: the addition of such small amounts of carbon and nitrogen compound forming elements can reduce iron loss and nonmagnetic aging. These microalloying elements, however, form fine precipitates with the C/N atoms in the steel, which strongly prevent grain growth during annealing. Therefore, the upper limit of the content of Nb+V+Ti microalloying elements in the invention is set to 0.0020 percent.
For high-grade non-oriented silicon steel, the content of [ Si ] + [ Al ] is higher, and a higher recrystallization driving force is needed, so that the annealing temperature is increased along with the increase of the content of [ Si ] + [ Al ], and both Si and Al are beneficial to promoting the growth of recrystallized grains and are beneficial to magnetism. However, mn lowers the transformation temperature, and thus the annealing temperature decreases as the [ Mn ] content increases. The recrystallization annealing temperature is not too low, and too low will be detrimental to the shape of the finished silicon steel sheet and also to the reduction of iron loss. The recrystallization annealing temperature is not too high, and too high will decrease the strength of the steel sheet.
When the recrystallization annealing temperature satisfies the formula (1), the grain size of the finished product after the final annealing is in the optimal size range of 100-150 μm, which is favorable for obtaining the unoriented silicon steel sheet with high frequency and low iron loss.
The soaking time of recrystallization annealing is 5-20s. The high temperature short time annealing is advantageous in promoting grain growth, and in addition, the annealing soaking time should be as short as possible in order to secure the strength of the steel sheet.
The annealing atmosphere of the soaking section adopts a partial pressure ratio of P (H) 2 O)/P(H 2 ) A non-oxidizing atmosphere of =0.0002 to 0.0005 is advantageous for preventing formation of an inner oxide layer and an inner nitride layer. If the annealing atmosphere is an oxidizing atmosphere, oxides are strongly formed on the surface of the steel sheet, which inhibit grain growth and increase iron loss.
When cooling down after annealing, the cooling speed is controlled at 7-10 ℃/s, so that the generation of larger internal stress can be avoided, and the iron loss can be reduced. The cooling speed is too high, and larger internal stress is easy to generate, so that the iron loss is increased.
Compared with the prior art, the method for manufacturing the non-oriented silicon steel for the new energy automobile driving motor can meet the requirements of high frequency and low iron loss of the non-oriented silicon steel material for the new energy automobile driving motor by controlling the recrystallization annealing procedure.
Detailed Description
In order that those skilled in the art will better understand the present invention, the present invention will be described in further detail with reference to specific embodiments.
Examples 1 to 8
(1) Smelting alloy and molten iron in a smelting furnace according to a proportion to obtain molten steel, wherein the composition of the molten steel is shown in a table 1;
(2) Smelting and continuously casting molten steel by a converter, and heating a casting blank to 1100-1220 ℃;
(3) After conventional hot rolling to a hot rolled plate with a thickness of 2.0mm, normalizing annealing is carried out at 900-1200 ℃ for 100-240s.
(4) Then cold rolling is carried out to the thickness of a finished product, and a non-oriented silicon steel plate with the thickness of 0.25+/-0.005 mm is obtained;
(5) Then, performing recrystallization annealing according to the process shown in Table 2; the recrystallization annealing treatment process comprises the steps of heating, soaking and cooling in the annealing process;
the annealing soaking temperature T and the Si, al and Mn contents in the steel have the following empirical relation:
230×([Si]+[Al]-[Mn])-20≤T≤240×([Si]+[Al]-[Mn])(1)
wherein T is annealing soaking temperature in unit DEG C; [ Si ] is the addition amount of Si in units; [ Al ] is the addition amount of Al in units; mn is the amount of Mn added in unit%.
The temperature rising speed in the recrystallization annealing process is 70-100 ℃/s, the soaking time in the recrystallization annealing is 5-20s, and the soaking time is shown in table 2;
the annealing atmosphere of the soaking section in the recrystallization annealing process adopts a partial pressure ratio of P (H 2 O)/P(H 2 ) A non-oxidizing atmosphere of =0.0002 to 0.0005, the specific partial pressure of the non-oxidizing atmosphere is shown in table 2;
when the temperature is reduced after recrystallization annealing, the cooling speed is controlled to be 7-10 ℃/s, and the cooling speed is shown in table 2;
(6) Finally, an insulating coating is coated, and the finished non-oriented silicon steel material is obtained after drying at 300-550 ℃.
Comparative examples 1 to 4
(1) Smelting alloy and molten iron in a smelting furnace according to a proportion to obtain molten steel, wherein the composition of the molten steel is shown in a table 1;
(2) Smelting and continuously casting molten steel by a converter, and heating a casting blank to 1100-1220 ℃;
(3) After conventional hot rolling to a hot rolled plate with a thickness of 2.0mm, normalizing annealing is carried out at 900-1200 ℃ for 100-240s.
(4) Then cold rolling is carried out to the thickness of a finished product, and a non-oriented silicon steel plate with the thickness of 0.25+/-0.005 mm is obtained;
(5) Then, performing recrystallization annealing according to the process shown in Table 2; the recrystallization annealing treatment process comprises the steps of heating, soaking and cooling in the annealing process;
the annealing soaking temperature T is shown in table 2;
the heating rate in the annealing process is 70-100 ℃/s, and the recrystallization annealing soaking time is shown in table 2;
the soaking section annealing atmosphere in the recrystallization annealing process adopts a non-oxidizing atmosphere, and the specific partial pressure ratio of the non-oxidizing atmosphere is shown in table 2;
when cooling down after recrystallization annealing, the cooling rate is shown in table 2;
(6) Finally, an insulating coating is coated, and the finished non-oriented silicon steel material is obtained after drying at 300-550 ℃.
TABLE 1 Components of molten steel (unit: mass%)
| Element(s) | C | Si | Al | Mn | P | S | N | V+Ti+Nb |
| Example 1 | 0.003 | 2.8 | 1.0 | 0.35 | 0.01 | 0.002 | 0.0015 | 0.002 |
| Example 2 | 0.0028 | 3.2 | 1.5 | 0.15 | 0.03 | 0.0018 | 0.0014 | 0.001 |
| Example 3 | 0.0029 | 2.9 | 1 | 0.15 | 0.02 | 0.0019 | 0.0013 | 0.0019 |
| Example 4 | 0.0027 | 3 | 1.2 | 0.2 | 0.01 | 0.002 | 0.0014 | 0.0018 |
| Example 5 | 0.003 | 3.1 | 1.3 | 0.25 | 0.02 | 0.0019 | 0.0015 | 0.001 |
| Example 6 | 0.0029 | 2.8 | 1.5 | 0.3 | 0.01 | 0.002 | 0.0013 | 0.002 |
| Example 7 | 0.0028 | 3.2 | 1 | 0.35 | 0.03 | 0.0018 | 0.0014 | 0.0015 |
| Example 8 | 0.003 | 3 | 1.4 | 0.22 | 0.015 | 0.0017 | 0.0014 | 0.0016 |
| Comparative example 1 | 0.003 | 2.8 | 1.5 | 0.18 | 0.03 | 0.002 | 0.0015 | 0.001 |
| Comparative example 2 | 0.0029 | 3.2 | 1.4 | 0.3 | 0.01 | 0.002 | 0.0014 | 0.0015 |
| Comparative example 3 | 0.0028 | 3 | 1 | 0.2 | 0.02 | 0.0018 | 0.0015 | 0.002 |
| Comparative example 4 | 0.0028 | 2.9 | 1.2 | 0.25 | 0.02 | 0.0018 | 0.0015 | 0.002 |
TABLE 2 Main Process parameters for the examples and comparative examples of the invention
It can be seen from Table 3 that when the recrystallization annealing process meets the scope of the technical proposal of the invention, a high grade non-oriented silicon steel product with excellent magnetism can be obtained, B 5000 1.710T, P 1.0/400 At 13.2w/kg。
Table 3 properties of steel products
From the experimental results of the comparative examples and examples, it can be seen that:
in comparative example 1, the annealing soaking temperature was 910 ℃, the formula (1) proposed in the present invention was not satisfied, the recrystallization annealing temperature was too low, resulting in poor plate shape of the silicon steel plate, poor magnetic properties of the steel plate, B 5000 1.571T, P 1.0/400 35.8w/kg.
In comparative example 2, soaking section P (H 2 O)/P(H 2 ) The partial pressure ratio is 0.0006, the partial pressure ratio is too high, oxide is easy to generate on the surface of the steel plate, the growth of crystal grains is prevented, the iron loss of the steel plate is increased, B 5000 1.576T, P 1.0/400 35.7w/kg.
In comparative example 3, the cooling rate after annealing was 11 ℃ per second, the cooling rate was too high, and large internal stress was generated in the steel sheet, causing deterioration of the magnetic properties of the steel sheet, B 5000 1.578T, P 1.0/400 35.9w/kg.
In comparative example 4, the temperature rise rate during annealing was 65 ℃ per second, which did not satisfy the annealing temperature rise rate proposed by the present invention, and the temperature rise rate was too slow, which was unfavorable for the growth of recrystallized grains, the magnetic properties of the steel sheet were poor, B 5000 1.578T, P 1.0/400 35.9w/kg.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (5)
1. A manufacturing method of high-frequency low-iron-loss non-oriented silicon steel for a new energy automobile driving motor is characterized by comprising the following steps:
(1) Smelting alloy and molten iron in a smelting furnace according to a proportion to obtain molten steel, wherein the molten steel comprises the following components in percentage by weight: c is less than or equal to 0.003 percent, si:2.8% -3.2%, al:1.0-1.5%, mn:0.15-0.35%, P:0.01-0.015%, S less than or equal to 0.0020%, N less than or equal to 0.0015%, V+Ti+Nb less than or equal to 0.0020%, and the balance of Fe and unavoidable impurities;
(2) Smelting and continuously casting molten steel by a converter, and heating a casting blank to 1100-1220 ℃;
(3) After conventional hot rolling to a hot rolled plate with the thickness of 2.0mm, carrying out normalizing annealing at 900-1200 ℃ for 100-240 s;
(4) Then cold rolling is carried out to the thickness of a finished product, and a non-oriented silicon steel plate with the thickness of 0.25+/-0.005 mm is obtained;
(5) Finally, carrying out recrystallization annealing; the recrystallization annealing treatment process comprises the steps of heating, soaking and cooling in the annealing process;
the temperature rising speed in the recrystallization annealing process is 70-100 ℃/s;
the annealing atmosphere of the soaking section in the recrystallization annealing process adopts a partial pressure ratio of P (H 2 O)/P(H 2 ) A non-oxidizing atmosphere of =0.0002 to 0.0005;
cooling after recrystallization annealing;
(6) Finally, an insulating coating is coated and dried at 300-550 ℃.
2. The method for manufacturing high-frequency low-iron-loss non-oriented silicon steel for a driving motor of a new energy automobile as claimed in claim 1, wherein:
the recrystallization annealing soaking temperature in the step (5) satisfies the following relation:
230×([Si]+[Al]-[Mn])-20≤T≤240×([Si]+[Al]-[Mn])(1)
wherein T is annealing soaking temperature in unit DEG C; [ Si ] is the addition amount of Si in units; [ Al ] is the addition amount of Al in units; mn is the amount of Mn added in unit%.
3. The method for manufacturing high-frequency low-iron-loss non-oriented silicon steel for a driving motor of a new energy automobile as claimed in claim 2, characterized by:
the soaking time of the recrystallization annealing process in the step (5) is 5-20s.
4. The method for manufacturing high-frequency low-iron-loss non-oriented silicon steel for a driving motor of a new energy automobile as set forth in claim 3, wherein:
the partial pressure ratio of the non-oxidizing atmosphere of the soaking section annealing atmosphere in the step (5) is P (H) 2 O)/P(H 2 )＝0.0002-0.0005。
5. The method for manufacturing high-frequency low-iron-loss non-oriented silicon steel for a driving motor of a new energy automobile as claimed in claim 4, wherein:
and (3) cooling in the step (5), wherein the cooling speed is controlled to be 7-10 ℃/s.
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