CN114107799A - High-strength silicon steel thin strip plate with excellent high-frequency electromagnetic performance and production process - Google Patents
High-strength silicon steel thin strip plate with excellent high-frequency electromagnetic performance and production process Download PDFInfo
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- 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
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- 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
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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Abstract
A high-strength silicon steel thin strip plate with excellent high-frequency electromagnetic performance comprises the following chemical components in percentage by weight: less than or equal to 0.0027 percent of C, less than or equal to 3.10 percent to 3.35 percent of Si, 0.80 percent to 1.2 percent of Als0.20 percent to 0.85 percent of Mn, less than or equal to 0.050 percent of P, less than or equal to 0.0020 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Ti, less than or equal to 0.0020 percent of V, 0.0050 percent to 0.080 percent of Nb0, and the balance of Fe and inevitable impurities. The non-oriented silicon steel strip product is used for manufacturing a driving motor of a new energy automobile, and has high strength and excellent medium-high frequency electromagnetic property.
Description
Technical Field
The invention relates to the field of metal materials, in particular to a high-strength silicon steel thin strip plate with excellent high-frequency electromagnetic performance and a production process thereof.
Background
The new energy automobile is a well-known development trend, and a driving motor of the new energy automobile has higher performance and characteristic requirements on the adopted electric steel sheet compared with the conventional product. For good driving experience, the motor needs high torque starting, and the driving current and the magnetic induction of the electrical steel strip used must be improved; in order to improve the energy conversion efficiency, the electrical steel used by the motor is required to have excellent magnetic properties, namely high magnetic induction under a medium-low magnetic field and low iron loss under a high frequency; the high running speed requires the high-speed running of the motor rotor (6000-15000 r/min), and the electrical steel sheets have high enough strength to resist the centrifugal force; for the permanent magnet driving motor widely applied nowadays, magnetic poles are embedded in the rotor, and the requirement for ensuring the strength of the rotor is also crucial; the strength is also one of important indexes for improving the magnetic flux density and reducing the stator and rotor gaps to require good punching performance. The special electrical steel products are required to be developed towards the characteristics of thinning, high strengthening, high magnetic induction, low loss and high frequency by combining the development of frequency conversion control and application technology and the design requirement of new energy motors.
The traditional magnetic silicon steel improves the strength and reduces the iron loss through the solid solution strengthening of elements such as Si, but the high Si content causes no rolling, and the high Si content causes the magnetic induction to be reduced; while the strength is effectively improved by various strengthening mechanisms such as solid solution, precipitation and the like, the magnetic performance is poor; in addition, because the ultra-low carbon steel of the electrical steel can not be strengthened through a phase transformation and dislocation strengthening mechanism, and in order to prevent hysteresis aging, interstitial solid solution strengthening can not be carried out either … … the research on the high-strength non-oriented electrical steel is started from 1980 at home and abroad, more than hundred high-strength non-oriented electrical steel patents are applied, and most of the high-strength non-oriented electrical steel patents are set up for covering and hiding true process technologies; the intensive technical route adopted by the products of each major manufacturer is related to the commercial confidentiality of each company, and the detailed research and development and report on the aspects are rarely published.
Patent analysis aiming at the silicon steel for the high-strength new energy automobile motor shows that: since the eighties of the last century, japan began to lay out high-strength non-oriented electrical steel, and representatives of japan mainly applied hundreds of patents on high-strength non-oriented electrical steel in the country or in other countries for new day iron, JFE, and sumitomo metals.
The following technical routes and ideas exist in the disclosed patents: solid solution strengthening mainly adopts Si, P, Mn and Ni, and also uses other alloy elements such as Cr, Mo, Cu, Ti and the like, and the grain size of the finished plate is generally properly controlled in order to achieve high strength; solid-solution Ti is adopted to enhance the {111) plane texture to improve the strength, but the electromagnetic performance is sacrificed; the main strengthening means adopted is the solid solution strengthening of elements such as P, Mn, Ni and the like, although P is an element with good eutectic strengthening effect, P is easy to form brittle fracture of the steel plate caused by grain boundary segregation, and the solid solution strengthening element contains expensive metal nickel, so that the alloy cost is obviously increased, and the rolling difficulty is increased; according to the method for adding Nb, Ti, V and Zr micro-alloy elements into non-oriented silicon steel, on one hand, fine carbide particles are formed to improve the strength through precipitation strengthening, on the other hand, recrystallization in annealing is inhibited through solid solution Nb, so that the recrystallization fraction is not more than 90%, the defects of cold working dislocation of the part are reserved, the strength is improved by … …, and a plurality of strengthening means are provided, which summarize the solid solution strengthening of P, Mn and Ni, the precipitation strengthening of the micro-alloy elements (Ti, Nb, V and Zr) and the like, the aging strengthening of Cu and the dislocation strengthening of incomplete recrystallization, but corresponding system process control routes and parameters are still absent, and the optimal process control window expression of high strength and good electromagnetic properties is not realized; and the component design is complex, and the production difficulty and the control difficulty are increased.
Disclosure of Invention
The invention aims to provide a silicon steel thin strip plate with excellent high-strength high-frequency electromagnetic performance and a production process thereof.
The invention provides a special steel product which is designed by combining multi-element main alloy elements and micro-alloy elements under the conventional process route, and has high strength characteristic (Rp)0.2: 450-550 MPa), is suitable for 10000-15000 rpm driving motors, and still has good electromagnetic performance under high frequency.
In order to achieve the purpose, the invention adopts the following technical scheme:
a high-strength silicon steel thin strip plate with excellent high-frequency electromagnetic performance comprises the following chemical components in percentage by weight: less than or equal to 0.0027 percent of C, 3.10 to 3.35 percent of Si, 0.80 to 1.2 percent of Als, 0.20 to 0.85 percent of Mn, less than or equal to 0.050 percent of P, less than or equal to 0.0020 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Ti, less than or equal to 0.0020 percent of V, 0.0050 to 0.080 percent of Nb, and the balance of Fe and inevitable impurities.
The thickness of the thin strip plate is 0.27-0.35 mm.
The thin strip plate yield strength: 450 to 550 MPa.
C: exerting the segregation and segregation of microalloy elements in the grain boundary; the finished product is controlled not to be decarburized, and the high-efficiency production is realized;
mn: strengthening elements, improving cold rolling and hot rolling processability, improving the resistivity of a steel plate matrix and improving eddy current loss;
nb: the added microalloy elements and the high-silicon steel ferrite are in a body-centered cubic crystal structure, so that lattice distortion is reduced in a coherent manner, and the influence on the control of a matrix crystal structure is reduced when a solid solution strengthening effect is exerted; strong carbonitride elements play a role in precipitation strengthening and inhibiting magnetic aging of products; the Nb (C, N) precipitates are spherical, the quantity and the size of the precipitates are controlled by combining a process, and the influence of conventional multi-prismatic carbonitride on magnetic domains and coercive force is avoided; the precipitates and the crystal boundary are segregated (segregated), so that the fine grain strengthening function is achieved, and the high-frequency hysteresis and the eddy current loss are reduced; in the precipitate thermal history process, the size and the corresponding density distribution of Nb (C, N) particles are controlled by a specific process, and the functions of fine grain strengthening, precipitation strengthening and grain boundary strengthening are respectively realized.
A production process of a silicon steel thin strip plate with excellent high-strength high-frequency electromagnetic performance comprises the following steps: molten iron desulfurization, converter smelting, RH refining, continuous casting, hot rolling, normalizing, acid cleaning, cold rolling, continuous furnace annealing, coating, performance inspection and packaging; the specific method comprises the following steps:
after the molten steel is smelted to a target component, the molten steel is cast into a blank by the existing protective casting measures;
1) when the steel is put into a heating furnace, hot charging is carried out on the plate blank, and the hot charging temperature is more than or equal to 550 ℃ (the composition and control of original precipitates under the condition of the steel grade; in preparation for maintaining or reducing conventional heating process time); the slab temperature of a soaking section of a hot-rolled slab heating furnace is 1000-1150 ℃ (the density distribution and the size of Nb (C, N) precipitates are further controlled), the hot-rolling finishing temperature is 780-830 ℃ (the temperature system is combined with rolling to form a hot-rolled slab with the thickness of 2.2-1.8 mm, the fine precipitation form of Nb (C, N) is further controlled by deformation precipitation), and the coiling temperature is 700-800 ℃ (uniform structure is prepared for a normalizing process);
2) controlling the temperature of the normalized plate to be 850-950 ℃, adjusting the in-furnace time through the process speed, and controlling the grain size before cold rolling to be 80-130 mu m; after normalization, the hot-rolled plate is quenched to below 550 ℃ in an aerial fog manner, the cooling speed is more than 300 ℃/min, and the size and the distribution interval of a precipitate are controlled;
3) cold rolling to the thickness of a finished product after acid cleaning; the continuous annealing furnace is adopted for production, the temperature of a rapid heating section is set to 1050-1180 ℃, the nucleation rate is increased, the temperature of a soaking section is set to 880-980 ℃, the protection of the full nitrogen dry atmosphere is carried out, the annealing process speed is set according to the furnace length, and the grain size is 6-3 grade.
The thickness of the hot rolled plate after final rolling in the step 1) is 2.2-1.8 mm.
Compared with the prior art, the invention has the beneficial effects that:
1) the product can be produced on the traditional production line on the basis of certain steel cleanliness control without modifying process equipment;
2) the product adopts a single microalloy strengthening element, and multiple strengthening functions are exerted through the product heat history, so that the production difficulty of a product system is reduced conveniently;
3) the contradiction between high-magnetic induction type and high-strength type thin strip products under the high-frequency magnetization condition is solved well, the optimal performance control relation is found, and the staged requirement of the development of a downstream new energy motor is met;
4) the production of different products can be relatively controlled by adjusting the heat treatment process of the product, and the electromagnetic performance of the product can be mutually judged with the electromagnetic performance of the conventional high-grade product, so that the organization difficulty of small-batch production of small varieties is reduced, and the production inventory pressure is reduced;
5) besides the application of the traditional full-process product, the method is more suitable for annealing after punching by special users, and can also increase the normal process and obtain more excellent electromagnetic performance.
Detailed Description
The following examples are intended to illustrate the invention in detail, and are intended to be a general description of the invention, and not to limit the invention.
Example 1:
the steel comprises the following chemical components in percentage by weight: 0.0025% of C, 3.31% of Si, 0.55% of Mn, 0.008% of P, 0.0013% of S, 1.08% of Als, 0.0015% of N, 0.0018% of Ti, 0.0015% of V, 0.055% of Nb and the balance of iron and inevitable impurities.
The production method comprises the following process steps:
a) smelting and continuous casting: smelting in a converter, carrying out RH vacuum refining treatment, controlling the components of molten steel according to the requirements, and casting into a plate blank with the thickness of 230 mm;
b) and (3) hot charging the plate blank, wherein the hot charging temperature is 610 ℃, the temperature of a soaking section of a hot rolling plate blank heating furnace is 1130 ℃, and the plate blank enters a finishing mill group for rolling after being initially rolled to 40 mm. The finish rolling temperature is 1010 ℃, the finish rolling temperature is 810 ℃, the coiling temperature is 720 ℃, and the thickness of the hot rolled plate is 2.1 mm;
c) normalizing the hot rolled plate, controlling the plate temperature at 910 ℃, adjusting the in-furnace time through the process speed, and controlling the grain size before cold rolling to be 120 mu m; after normalizing, the hot-rolled plate is quenched to 550 ℃ in an aerial fog mode, the cooling speed is 320 ℃/min, and the size and the distribution interval of precipitates are controlled; cold rolling to 0.35mm after acid cleaning;
d) annealing process: the soaking section controls the temperature relatively high to produce the high magnetic induction type products; the soaking section realizes the product with high-strength type as the main requirement at relatively low temperature.
High-strength type: after cold rolling, the temperature of a continuous annealing rapid heating section is 1100 ℃, the temperature of a soaking section is 930 ℃, the total nitrogen protection is carried out, the process speed is 100m/min, the continuous annealing is carried out, and the grade of the grain structure is 5.5;
example 2:
the steel comprises the following chemical components in percentage by weight: 0.0023% of C, 3.28% of Si, 0.50% of Mn, 0.012% of P, 0.0013% of S, 0.98% of Als, 0.0016% of N, 0.0018% of Ti, 0.0017% of V, 0.058% of Nb, and the balance of Fe and inevitable impurities.
The production method comprises the following process steps:
a) smelting and continuous casting: smelting in a converter, carrying out RH vacuum refining treatment, controlling the components of molten steel according to the requirements, and casting into a plate blank with the thickness of 230 mm;
b) and (3) hot charging the plate blank, wherein the hot charging temperature is 600 ℃, the temperature of a soaking section of a hot rolling plate blank heating furnace is 1135 ℃, and the plate blank enters a finishing mill group for rolling after being initially rolled to 45 mm. The finish rolling start temperature is 1015 ℃, the finish rolling temperature is 820 ℃, the coiling temperature is 730 ℃, and the thickness of the hot rolled plate is 2.2 mm;
c) normalizing the hot rolled plate, controlling the plate temperature at 920 ℃, adjusting the in-furnace time through the process speed, and controlling the grain size before cold rolling to be 125 mu m; after normalizing, the hot-rolled plate is quenched to 550 ℃ in an aerial fog mode, the cooling speed is 310 ℃/min, and the size and the distribution interval of precipitates are controlled; cold rolling to 0.35mm after acid cleaning;
d) annealing process: the soaking section controls the temperature relatively high to produce the high magnetic induction type products; the soaking section realizes the product with high-strength type as the main requirement at relatively low temperature.
High-strength type: after cold rolling, the temperature of a continuous annealing rapid heating section is 1150 ℃, the temperature of a soaking section is 940 ℃, the total nitrogen protection is carried out, the process speed is 100m/min, the continuous annealing is carried out, and the grade of the grain structure is 5.5;
the contrast ratio is high magnetic induction type: after cold rolling, the temperature of a continuous annealing rapid heating section is 1080 ℃, the temperature of a soaking section is 970 ℃, the temperature is protected by total nitrogen, the process speed is 100m/min, the continuous annealing is carried out, and the grade of the grain structure is 4.5.
The product performance index pairs for different annealing processes are shown in table 1.
TABLE 1 comparison of annealing temperature and Performance between high magnetic induction type products and high strength type products of examples 1-2
Example 3:
the steel comprises the following chemical components in percentage by weight: 0.0025% of C, 3.26% of Si, 0.65% of Mn, 0.010% of P, 0.0008% of S, 1.05% of Als, 0.0016% of N, 0.0017% of Ti, 0.0019% of V, 0.055% of Nb and the balance of iron and inevitable impurities.
The production method comprises the following process steps:
a) smelting and continuous casting: smelting in a converter, carrying out RH vacuum refining treatment, controlling the components of molten steel according to the requirements, and casting into a plate blank with the thickness of 230 mm;
b) and (3) hot charging the plate blank, wherein the hot charging temperature is 650 ℃, the temperature of a soaking section of a hot rolling plate blank heating furnace is 1120 ℃, and the plate blank enters a finishing mill group for rolling after being initially rolled to 40 mm. The finish rolling start temperature is 1000 ℃, the finish rolling temperature is 790 ℃, the coiling temperature is 700 ℃, and the thickness of the hot rolled plate is 2.0 mm;
c) normalizing the hot rolled plate, controlling the plate temperature to be 900 ℃, adjusting the in-furnace time through the process speed, and controlling the grain size to be 110 mu m before cold rolling; after normalizing, the hot-rolled plate is quenched to 500 ℃ in an aerial fog mode, the cooling speed is 320 ℃/min, and the size and the distribution interval of precipitates are controlled; cold rolling to 0.27mm after acid cleaning;
d) annealing process: the soaking section controls the temperature relatively high to produce the high magnetic induction type products; the soaking section realizes the product with high-strength type as the main requirement at relatively low temperature.
High-strength type: after cold rolling, the temperature of a continuous annealing rapid heating section is 1120 ℃, the temperature of a soaking section is 910 ℃, the temperature is protected by total nitrogen, the process speed is 90m/min, the continuous annealing is carried out, and the grade of the grain structure is 5.5;
example 4:
the steel comprises the following chemical components in percentage by weight: 0.0024% of C, 3.25% of Si, 0.63% of Mn, 0.011% of P, 0.0008% of S, 1.02% of Als, 0.0016% of N, 0.0018% of Ti, 0.0015% of V, 0.065% of Nb, and the balance of iron and inevitable impurities.
The production method comprises the following process steps:
a) smelting and continuous casting: smelting in a converter, carrying out RH vacuum refining treatment, controlling the components of molten steel according to the requirements, and casting into a plate blank with the thickness of 230 mm;
b) and (3) hot charging the plate blank, wherein the hot charging temperature is 630 ℃, the temperature of the soaking section of the hot rolling plate blank heating furnace is 1130 ℃, and the plate blank enters a finishing mill group for rolling after being initially rolled to 40 mm. The finish rolling temperature is 1010 ℃, the finish rolling temperature is 800 ℃, the coiling temperature is 720 ℃, and the thickness of the hot rolled plate is 2.0 mm;
c) normalizing the hot rolled plate, controlling the plate temperature at 910 ℃, adjusting the in-furnace time through the process speed, and controlling the grain size to be 115 mu m before cold rolling; after normalizing, the hot-rolled plate is quenched to 500 ℃ in an aerial fog mode, the cooling speed is 320 ℃/min, and the size and the distribution interval of precipitates are controlled; cold rolling to 0.27mm after acid cleaning;
d) annealing process: the soaking section controls the temperature relatively high to produce the high magnetic induction type products; the soaking section realizes the product with high-strength type as the main requirement at relatively low temperature.
High-strength type: after cold rolling, the temperature of a continuous annealing rapid heating section is 1130 ℃, the temperature of a soaking section is 920 ℃, the total nitrogen protection is carried out, the process speed is 95m/min, the continuous annealing is carried out, and the grade of the grain structure is 5.5;
the contrast ratio is high magnetic induction type: after cold rolling, the temperature of a continuous annealing rapid heating section is 1080 ℃, the temperature of a soaking section is 960 ℃, the temperature is protected by total nitrogen, the process speed is 90m/min, the continuous annealing is carried out, and the grade of the grain structure is 4.0;
the product performance index pairs for different annealing processes are shown in table 2.
TABLE 2 comparison of annealing temperature and Performance between high magnetic induction type products and high strength type products of examples 3-4
Claims (5)
1. The high-strength silicon steel thin strip plate with excellent high-frequency electromagnetic performance is characterized in that the steel comprises the following chemical components in percentage by weight: less than or equal to 0.0027 percent of C, 3.10 to 3.35 percent of Si, 0.80 to 1.2 percent of Als, 0.20 to 0.85 percent of Mn, less than or equal to 0.050 percent of P, less than or equal to 0.0020 percent of S, less than or equal to 0.0020 percent of N, less than or equal to 0.0020 percent of Ti, less than or equal to 0.0020 percent of V, 0.0050 to 0.080 percent of Nb, and the balance of Fe and inevitable impurities.
2. The silicon steel thin strip plate with excellent high-strength high-frequency electromagnetic performance as claimed in claim 1, wherein the thickness of the thin strip plate is 0.27-0.35 mm.
3. The silicon steel thin strip plate with excellent high-strength high-frequency electromagnetic performance as claimed in claim 1, wherein the thin strip plate Rp is characterized in that0.2：450～550MPa。
4. A process for producing a silicon steel strip sheet excellent in high-strength high-frequency electromagnetic properties according to any one of claims 1 to 3, comprising:
1) when the plate blank is fed into a heating furnace, hot charging is carried out, and the hot charging temperature is more than or equal to 550 ℃; the slab temperature of a soaking section of a hot-rolled slab heating furnace is 1000-1150 ℃, the hot-rolled finish rolling temperature is controlled to be 780-830 ℃, and the coiling temperature is 700-800 ℃;
2) controlling the normalized plate temperature to be 850-950 ℃, and controlling the grain size before cold rolling to be 80-130 mu m; after normalizing, the hot-rolled plate is quenched to below 550 ℃ in an aerial fog manner, and the cooling speed is more than 300 ℃/min;
3) the production is carried out by adopting a continuous annealing furnace, the temperature of a rapid heating section is set to be 1050-1180 ℃, the temperature of a soaking section is set to be 880-980 ℃, and the full nitrogen dry atmosphere protection meets the grain size of 3-6 grades.
5. The production process of the silicon steel thin strip plate with excellent high-strength high-frequency electromagnetic performance according to claim 4, characterized in that the thickness of the hot rolled plate after final rolling in the step 1) is 1.8-2.2 mm.
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| CN115198198A (en) * | 2022-09-13 | 2022-10-18 | 张家港扬子江冷轧板有限公司 | Non-oriented silicon steel for high-speed motor and preparation method thereof |
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| CN115198198B (en) * | 2022-09-13 | 2022-12-23 | 张家港扬子江冷轧板有限公司 | Non-oriented silicon steel for high-speed motor and preparation method thereof |
| WO2024055269A1 (en) * | 2022-09-13 | 2024-03-21 | 张家港扬子江冷轧板有限公司 | Non-oriented silicon steel for high-speed motor, and manufacturing method therefor |
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