CN114717480A - B8Moderate-temperature common oriented silicon steel with temperature not less than 1.90T and manufacturing method thereof - Google Patents
B8Moderate-temperature common oriented silicon steel with temperature not less than 1.90T and manufacturing method thereof Download PDFInfo
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- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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Abstract
The invention discloses a8Medium-temperature common oriented silicon steel of not less than 1.90T and a manufacturing method thereof. The oriented silicon steel comprises the following chemical components in percentage by weight: c: 0.020% to 0.060%, Si: 2.80% -3.50%, Als: 0.010-0.0 percent35%, N: 0.0060-0.0110%, Mn: 0.15% -0.30%, S: 0.0030 to 0.0100%, Cu: 0.40 to 0.60 percent of the total weight of the alloy, less than or equal to 0.020 percent of P, V, Nb, B, Mo, Ti and Ca, less than or equal to 0.030 percent of (V + Nb + B + Mo + Ti + Ca), and the balance of iron and inevitable impurities. According to the invention, through the optimization of the component proportion and parameters of the steel grade, the magnetic induction intensity of the obtained common oriented silicon steel reaches the range of high-magnetic induction oriented silicon steel.
Description
Technical Field
The invention relates to common oriented silicon steel and a manufacturing method thereof, in particular to B8Medium-temperature common oriented silicon steel of not less than 1.90T and a manufacturing method thereof.
Background
The oriented silicon steel can be divided into common oriented silicon steel (CGO) and high magnetic induction oriented silicon steel (Hi-B) according to performance conditions, wherein the common oriented silicon steel can be divided into high-temperature heating oriented silicon steel (slab heating temperature is 1350-1400 ℃) and medium-temperature heating oriented silicon steel (slab heating temperature is 1250-1320 ℃) according to slab heating temperature.
The traditional high-temperature slab heating technology needs to heat the slab to 1350-1400 ℃, and the slab needs to be kept at the temperature for 4-5 hours. Under these conditions, the slab surface reacts with air to form fayalite (Fe)2SiO4) The oxides (melting point down to 1300 c) which, after heating, run down the slab surface and a portion accumulates in the refractory material inside the furnace, so that after a certain number of continuous operations the lining must be repaired. In a steel plant requiring continuous operation, there are caused a reduction in working efficiency and productivity, and an increase in manufacturing cost. Therefore, the heating temperature of the common oriented silicon steel is reduced to 1250-1280 ℃ by adjusting the components of the steel grade, so that the interference can be eliminated, and other advantages are obtained.
The cores of single-phase and three-phase transformers made of CGO steel and Hi-B steel prove that the cores made of Hi-B steel have low loss, but the assembly factor is 5% -20% higher than that of the cores made of CGO steel, and Hi-B steel is not exertedThe magnetic advantage of (1). Therefore, it is of far-reaching significance to improve the magnetic performance of the CGO steel so as to exert the advantages of the CGO steel in iron core assembly. However, the magnetic induction B of CGO steel8Generally understood to be below 1.89T, cannot meet the increasing needs of users. Aiming at the weakness, a preparation method capable of improving the magnetic induction strength of the CGO steel is urgently needed.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a B8Medium-temperature common oriented silicon steel of not less than 1.90T and a manufacturing method thereof. The invention obtains higher magnetic induction intensity (B) by adjusting the component proportion of the steel grade and optimizing the process parameters8Not less than 1.90T), the magnetic induction intensity reaches the range of high magnetic induction oriented silicon steel, and the harsh preparation process of the high magnetic induction oriented silicon steel is avoided.
The technical scheme of the invention is as follows:
b8The medium-temperature common oriented silicon steel is not less than 1.90T, and the medium-temperature common oriented silicon steel comprises the following chemical components in percentage by weight: c: 0.020% to 0.060%, Si: 2.80% -3.50%, Als: 0.010% -0.035%, N: 0.0060-0.0110%, Mn: 0.15% -0.30%, S: 0.0030 to 0.0100%, Cu: 0.40 to 0.60 percent of the total weight of the alloy, less than or equal to 0.020 percent of P, V, Nb, B, Mo, Ti and Ca, less than or equal to 0.030 percent of (V + Nb + B + Mo + Ti + Ca), and the balance of iron and inevitable impurities.
Further, the medium-temperature common oriented silicon steel comprises the following chemical components in percentage by weight: c: 0.020% to 0.060%, Si: 2.80% -3.50%, Als: 0.015% -0.030%, N: 0.0075-0.0090%, Mn: 0.19% -0.25%, S: 0.0050-0.0080%, Cu: 0.45 to 0.55 percent of the total weight of the alloy, less than or equal to 0.020 percent of P, V, Nb, B, Mo, Ti and Ca, less than or equal to 0.030 percent of (V + Nb + B + Mo + Ti + Ca), and the balance of iron and inevitable impurities.
Further, the final thickness of the medium-temperature oriented silicon steel is 0.23mm, and the magnetic induction intensity B of the medium-temperature oriented silicon steel8Not less than 1.90T, iron loss P1.7/50≤0.950W/kg。
The preparation method of the medium-temperature common oriented silicon steel comprises the following steps:
1) smelting molten steel and continuously casting into a casting blank;
2) heating a casting blank to carry out hot rolling, wherein the heating temperature of the casting blank is 1250-1320 ℃; the finishing temperature is 900-1020 ℃, and the thickness of the hot rolled plate is 2.20-2.40 mm;
3) coiling, wherein the coiling temperature is controlled to be 500-600 ℃;
4) carrying out one-time cold rolling after conventional pickling, and controlling the rolling reduction rate to be 70-75%;
5) performing intermediate complete decarburization annealing and secondary cold rolling on the steel strip subjected to the cold rolling in the step (4), and controlling the reduction rate of the secondary cold rolling to be 60-65%; the decarburization annealing temperature is 790-860 ℃, the heat preservation time is 360s, and the protective atmosphere is H2And N2In the wet mixed gas of (2), wherein H2The volume content is 17-26%; the protective atmosphere is characterized in that the temperature of the water in the humidifier is adjusted to control the dew point of the atmosphere in the furnace to be 43-51 ℃;
6) coating an annealing release agent which takes MgO as a main component;
7) high-temperature purification annealing;
8) stretching, flattening, coating an insulating coating, and laser scoring to obtain B81.90T or more medium-temperature common oriented silicon steel.
Further, in the step (2), the heating temperature of the casting blank is 1250-1280 ℃.
Further, in the step (5), the decarburization annealing is carried out by raising the temperature to the decarburization annealing temperature at a speed of 10-15 ℃/s and then keeping the temperature for 360 s.
Further, in the step (5), the speed of discharging and cooling the steel strip after decarburization and annealing is more than or equal to 20 ℃/s.
Further, in the step (5), the temperature of decarburization annealing is 800-850 ℃, and the heat preservation time is 360 s; the protective atmosphere is H2And N2In the wet mixed gas of (2), wherein H2The volume content is 19-22%.
Further, in the step (5), the specific process of controlling the water temperature of the humidifier is as follows: controlling the water temperature of a humidifier to be 43-46 ℃ for 0-194 s of decarburization annealing; 194-284 s, and controlling the water temperature of the humidifier to be 46-49 ℃; 284-360 s, and controlling the water temperature of the humidifier to be 43-46 ℃.
Further, in the step (5), the oxygen content of the steel strip after decarburization annealing is not less than 700ppm, and the carbon content is not more than 25 ppm.
The components and the main process action and mechanism of the invention are as follows:
c and carbon are important elements for manufacturing the oriented silicon steel. The carbon specification of the CGO steel is 0.03-0.05%, and the main purpose of ensuring the content of the CGO steel not to be less than 0.03% before the decarburization process is as follows: a. the smelting operation is easy, the steel recovery rate is improved, and the service life of a furnace lining is prolonged; b. improving the transverse crack of hot and cold rolled sheets; c. after C silicon steel with the concentration of more than 0.03 percent is subjected to hot rolling, cooling and coiling at the temperature of 550 ℃, dispersed Fe is separated out from a hot rolled plate3C, hindering the primary crystal grain from growing; d. the existence of 20-30% of gamma phase in the hot rolling process is ensured, the hot rolled plate structure is refined and is layered fine deformation crystal grains and small recrystallization crystal grains, and primary crystal grains are fine and uniform after decarburization and annealing; e. too high a carbon content causes difficulty in decarburization. The carbon is removed after the cold rolling to the thickness of the finished product, and the main purpose is to ensure that the product is in a single alpha phase during subsequent high-temperature annealing so as to develop perfect secondary recrystallization and eliminate the magnetic aging of the product.
Si and Si mainly play roles in oriented silicon steel in reducing iron loss and improving resistivity, but when phase change occurs in the hot rolling process, silicon has the tendency of being segregated along grain boundaries, so that the silicon is brittle in processing. Therefore, when the silicon content is increased to 3.2-3.4%, a small amount of copper, tin, antimony or molybdenum is added to the steel to further enhance the inhibition capability. The silicon content in the CGO steel is determined to be 2.80-3.40%.
Al and N are elements that form favorable inhibitors of AlN. According to the invention, AlN is used as a main inhibitor, so that the heating temperature of a casting blank is emphasized to be 1250-1320 ℃, AlN is fully dissolved, and fine AlN is precipitated in the hot rolling and annealing processes, so that primary crystal grains after decarburization and annealing are finer and more uniform. The invention controls the content of Als to be 0.010 to 0.035 percent and the content of N to be 0.0060 to 0.0110 percent; preferably: and Als: 0.015% -0.030%, N: 0.0075-0.0090%.
Mn, S and MnS are main inhibitors for heating the CGO steel at high temperature, and the heating temperature of a casting blank is required to reach 1350-1400 ℃. The invention takes AlN as a main inhibitor, and the main effect of adding Mn element reduces the eddy current loss, thereby controlling the Mn content to be 0.15-0.30 percent and the S content to be 0.0030-0.0100 percent; preferably: mn: 0.19% -0.25%, S: 0.0050-0.0080%.
Cu is an auxiliary inhibitor forming element of the invention, and the content of Cu is controlled to be 0.40-0.60%; preferably: cu: 0.45 to 0.55 percent.
P is taken as an impurity element, and is controlled to be less than or equal to 0.020%.
V, Nb, B, Mo, Ti and Ca which are supplementary inhibitor forming elements, and the total amount of the elements is less than or equal to 0.030 percent.
The heating temperature of the casting blank is controlled to 1250-1320 ℃, and the nitriding treatment is not carried out subsequently, so that the complete solid solution of the intrinsic inhibitor AlN is promoted (the AlN solid solution temperature is about 1200 ℃). The heating temperature should not be too high, thereby preventing coarsening of crystal grains and increasing energy consumption. Preferably: the heating temperature of the casting blank is 1250-1280 ℃.
The finishing temperature is controlled to be 900-1020 ℃, the hot rolling is ensured to be carried out in a higher temperature region range, the higher finishing temperature is ensured, the coarsening of second phase particles such as AlN and the like in the hot rolling process is prevented, and the edge crack and the surface defect of the hot ribbon are prevented.
The invention controls the coiling temperature to be 500-600 ℃, so that the carbide can be dispersed and distributed in the crystal grains, and fine and uniform primary crystal grains can be obtained later.
The invention controls the one-time cold rolling reduction rate to be 70-75%, and firstly ensures the proper reduction rate of the final product; secondly, the Goss texture disappears completely when the reduction ratio is too high, and the uniform and fine primary recrystallized structure cannot be obtained when the reduction ratio is too low.
The invention controls the temperature of decarburization annealing to be 790-860 ℃, the heat preservation time to be 360s, controls the dew point in the furnace to be 43-51 ℃ by adjusting the water temperature of the humidifier, and controls the protective atmosphere to be H2And N2Of wet mixed gas of (2), wherein H2The volume content is 17-26%, and the purpose is to complete primary recrystallization and make the matrix have enough [110 ]](001) Grains and favour their growthPrimary recrystallized structure and texture of (a); the carbon in the steel is removed to be below 0.0030 percent, and the high-temperature annealing is ensured to be in a single alpha phase; a compact and uniform oxide film structure is obtained on the surface of the steel strip. Preferably: controlling the temperature rise speed of the steel in the rapid heating section to be 10-15 ℃/s before the steel is brought into the furnace; controlling the decarburization annealing temperature at 800-850 ℃; the atmosphere in the furnace is wet nitrogen-hydrogen mixed gas, wherein the volume of the hydrogen accounts for 19-22%; controlling the oxidizing atmosphere to perform decarburization annealing according to the combination of increasing and decreasing of the water temperature of each section of the humidifier in the furnace, wherein: controlling the water temperature of a humidifier to be 43-46 ℃ within the first 0-194 s of decarburization annealing; controlling the water temperature of the humidifier to be 46-49 ℃ in 194-284 s of annealing time; controlling the water temperature of the humidifier to be 43-46 ℃ in 284-360 s of annealing time; controlling the cooling speed to be not lower than 20 ℃/h after the steel strip is taken out of the furnace; the oxygen content of the decarburized steel strip is controlled to be not less than 700ppm, and the carbon content is not more than 25 ppm.
The invention controls the secondary cold rolling reduction rate to be 60-65%, and aims to control the good inhibition effect of the inhibitor and stabilize the magnetic property of the final product.
The beneficial technical effects of the invention are as follows:
1. the invention increases the oxygen content of the medium-temperature common oriented silicon steel decarburization plate to be not less than 700ppm at least on the premise of not changing the existing production process and steel components, and obtains a thicker oxide layer and a finished bottom layer.
2. The inhibitor of the main body of the grain growth selects AlN (the solid solution temperature is 1200 ℃), and the auxiliary inhibitor is Cu2S, the precipitation of MnS (solution temperature 1280 ℃ C.) during the heating of a normal high-temperature slab is suppressed as much as possible. Therefore, the precipitation of MnS is inhibited by limiting the S content to 0.0030-0.0100% (preferably 0.0050-0.0080%), reducing the heating temperature of the casting blank to 1250-1320 ℃ (preferably 1250-1280 ℃).
3. The magnetic induction intensity of the medium-temperature oriented silicon steel prepared by the invention is improved to at least not less than 1.90T from the existing 1.88T, the magnetic induction intensity reaches the range of high-magnetic-induction oriented silicon steel, the harsh preparation process of the high-magnetic-induction oriented silicon steel is avoided, the difference of the magnetic characteristics among products is very small, the magnetic characteristics among the products are uniform, the operation is simple, and the implementation is very easy.
Drawings
FIG. 1 is a schematic view of an oxide layer after decarburization annealing in example 1 of the present invention.
FIG. 2 is a photograph showing the morphology of grains in finished silicon steel in accordance with example 1 of the present invention.
Detailed Description
The present invention will be described in detail with reference to the accompanying drawings and examples.
Examples 1 to 5
Embodiments 1-5 of the present invention provide a compound B8The components and the weight percentage of the oriented silicon steel in the embodiments 1 to 5 are shown in the table 1, except the components in the table, the rest is iron and inevitable impurities.
Table 1 list of the components and percentages by weight (%)
Examples 1 to 5 described B8The medium-temperature common oriented silicon steel with the temperature not less than 1.90T is manufactured according to the following steps:
1) smelting molten steel and continuously casting into a casting blank;
2) heating a casting blank, wherein the heating temperature is controlled to be 1250-1320 ℃;
3) hot rolling, wherein the finishing temperature is controlled to be 900-1020 ℃;
4) coiling, wherein the coiling temperature is controlled to be 500-600 ℃;
5) carrying out one-time cold rolling after conventional pickling, and controlling the rolling reduction rate to be 70-75%;
6) intermediate complete decarburization annealing, wherein the decarburization annealing is carried out by controlling the oxidizing atmosphere in a way of combining the increasing and decreasing of the water temperature of each section of the humidifier in the furnace, and the temperature and the degree of the decarburization annealing are keptThe temperature and time are shown in Table 2, and the protective atmosphere is H2And N2In the wet mixed gas of (2), wherein H2The volume content is controlled to be 17-26 percent; the dew point is controlled to be 43-51 ℃ by adjusting the water temperature of the humidifier, the water temperature of the humidifier is controlled to be in the range of 0-194 s, 194-284 s and 284-360 s before decarburization annealing, and the water temperature is controlled as shown in a table 2; the decarburization annealing temperature is 790-860 ℃, the heat preservation time is 360s, the furnace is controlled by adjusting the water temperature of a humidifier, and the protective atmosphere is H2And N2The wet mixed gas of (4);
7) secondary cold rolling, and controlling the rolling reduction rate to be 60-65%;
8) coating high-temperature annealing release agent with MgO as main component, wherein the MgO coating amount of the upper and lower plate surfaces is controlled to be 5-9 g/m2Controlling the water content to be 1.5% -2%;
9) high-temperature purification annealing: firstly at H2：N23: 1, heating to 680 ℃ at a speed of 60 ℃/H, preserving heat for 30H, heating to 1200 ℃ at a speed of 13 ℃/H in the atmosphere, and switching to pure H2Then preserving heat for 24 h;
10) stretching and flattening and coating an insulating coating;
11) and (4) laser scoring.
The main process parameters of examples 1-5 are shown in table 2.
Table 2 list of main process parameters of various embodiments of the present invention
The coating amounts of the high-temperature annealing release agents in examples 1 to 5 were 7.79g/m, respectively2、5.92g/m2、6.74g/m2、8.04g/m2、6.33g/m2The water content is controlled to be 1.85%, 1.68%, 1.92%, 1.81% and 1.58%.
Comparative examples 1 to 5
Comparative examples 1 to 5 respectively provide medium-temperature ordinary oriented silicon steel and a manufacturing method thereof, the components and weight percentages of the oriented silicon steel of comparative examples 1 to 5 are shown in table 3, and the rest are iron and inevitable impurities except the components in the table.
TABLE 3 tabulation of the compositions and weight percentages (%)
| Comparative example | C | Si | Als | N | | S | Cu | |
| 1 | 0.047 | 3.20 | 0.034 | 0.0112 | 0.20 | 0.0055 | 0.52 | |
| 2 | 0.039 | 3.05 | 0.024 | 0.0083 | 0.23 | 0.0053 | 0.49 | |
| 3 | 0.043 | 3.09 | 0.012 | 0.0058 | 0.22 | 0.0065 | 0.53 | |
| 4 | 0.040 | 3.08 | 0.022 | 0.0084 | 0.20 | 0.0052 | 0.51 | |
| 5 | 0.041 | 3.13 | 0.024 | 0.0081 | 0.22 | 0.0063 | 0.51 | |
| Comparative example | P | V | Nb | B | | Ti | Ca | |
| 1 | 0.0093 | 0.001 | 0.002 | 0.0001 | 0.0012 | 0.0017 | 0.0004 | |
| 2 | 0.0087 | 0.002 | 0.002 | 0.0003 | 0.0008 | 0.0011 | 0.0002 | |
| 3 | 0.0124 | 0.003 | 0.002 | 0.0002 | 0.0011 | 0.0006 | 0.0003 | |
| 4 | 0.0079 | 0.002 | 0.003 | 0.0002 | 0.0003 | 0.0009 | 0.0002 | |
| 5 | 0.0257 | 0.012 | 0.012 | 0.0015 | 0.0021 | 0.0034 | 0.0023 |
Comparative examples 1 to 5 the medium temperature ordinary oriented silicon steel was manufactured according to the following steps, and the specific process parameters of each comparative example are shown in table 4:
1) smelting molten steel and continuously casting into a casting blank;
2) heating the casting blank, and controlling the heating temperature;
3) hot rolling and controlling the finishing temperature;
4) coiling and controlling the coiling temperature;
5) carrying out primary cold rolling after conventional pickling, and controlling the rolling reduction rate as shown in table 4;
6) performing intermediate complete decarburization annealing, controlling the oxidation atmosphere to perform decarburization annealing in a way of combining increasing and decreasing of water temperature of each section of humidifier in the furnace, wherein the decarburization annealing temperature and the heat preservation time are shown in Table 4, and the protective atmosphere is H2And N2In the wet mixed gas of (2), wherein H2The volume content is 17-26%; controlling the dew point in the furnace to be 43-51 ℃ by adjusting the water temperature of the humidifier, and controlling the water temperatures of the humidifier in the first 0-194 s, 194-284 s and 284-360 s of decarburization annealing as shown in Table 4;
7) secondary cold rolling, and controlling the rolling reduction rate;
8) coating a high-temperature annealing separant taking MgO as a main component, wherein the MgO coating amount and the water content control parameters are the same as those of the invention example;
9) high-temperature purification annealing, wherein the annealing process is the same as that of the invention example;
10) stretching and flattening and coating an insulating coating;
11) and (4) laser scoring.
The main process parameters of comparative examples 1-5 are shown in table 4.
Table 4 list of main process parameters of comparative examples 1 to 5 according to the invention
The coating amounts of the high-temperature annealing release agents in comparative examples 1 to 5 were 6.74g/m, respectively2、7.03g/m2、6.67g/m2、5.28g/m2、7.10g/m2The water content is controlled to be 1.72%, 1.91%, 1.78%, 1.89% and 1.63%.
Test example:
the HW2000 high frequency infrared carbon sulfur analyzer, LECO O/N736 oxygen nitrogen analyzer and glow discharge spectrometer (HORIBA) are used to respectively determine the carbon content, oxygen content and oxide layer thickness after decarburization process in the preparation of the oriented silicon steel of the examples 1-5 and the comparative examples 1-5, and a magnetic performance measuring instrument (TD 8510 constant in Changsha) is used to determine the magnetic induction intensity and iron loss of the finished silicon steel, and the results are shown in Table 5.
TABLE 5 decarburization annealing process effects and final product properties of examples and comparative examples of the present invention
As is clear from tables 1, 3 and 5, the ranges of the respective elemental compositions of examples 1 to 5 and comparative examples 2 and 4 fall within the preferable elemental content ranges; the contents of Als and N elements of comparative examples 1 and 3 are respectively slightly higher and slightly lower than the preferable range, wherein the contents of Als and N in the comparative example 1 are slightly higher, the AlN precipitation amount is increased after the plate blank is heated, and the inhibition force is increased in high-temperature annealing; in the comparative example 3, the content of Als and N is low, the precipitation amount of AlN is reduced after the plate blank is heated, and the inhibition force is reduced in high-temperature annealing; in the comparative example 5, P is more than 0.020%, and (V + Nb + B + Mo + Ti + Ca) is more than 0.030%, the content of interface enrichment elements is too high, hot rolling edge cracks are extremely large, and the production is difficult to smoothly carry out.
As can be seen from tables 2, 4 and 5, the heating temperature of the plate blank of comparative example 2 exceeds the specified upper limit temperature of 1320 ℃, and the crystal grain size of the casting blank grows, so that the crystal grain sizes of the hot rolled plate and the primary recrystallization annealed plate grow; meanwhile, the heating temperature is higher, so that the solid solution amount of the MnS inhibitor is increased, the level of the inhibitor is too high, the grain size of a finished product is smaller, and the magnetic property is reduced; in addition, the heating temperature is too high, the burning loss of the casting blank is increased, and the yield is reduced. Comparative example 1 the suppression ability was too strong due to the excessive amount of the inhibitor, the development of secondary recrystallization was incomplete, and the magnetic properties were reduced; comparative example 3 the magnetic properties of the final product were reduced due to the reduced amount of inhibitor, reduced inhibition ability, and oversized secondary grains; comparative example 2 the heating temperature was too high, the level of inhibitor and primary grain size did not match, and the magnetic properties decreased; comparative example 4 the water temperature of the humidifier at the front section of the decarburization annealing process is too high, so that the oxidizing atmosphere at the front section is increased, the formation speed of the oxide film is increased, the decarburization retarding rate is accelerated, and the decarburization effect is reduced; in addition, the number of Gaussian textures is insufficient, so that the magnetic property is reduced; comparative example 3 has too high content of interfacial segregation elements to deteriorate magnetic properties.
FIG. 1 is a schematic view of an oxide layer after decarburization annealing in example 1 of the present invention. In the figure, the vertical direction is the Normal Direction (ND), the horizontal direction is the Rolling Direction (RD), and the starting point of the oxide layer thickness proceeds from the steel substrate as the starting point. As can be seen from FIG. 1, the oxide film of example 1 has a uniform thickness of about 6.2 to 7.7 μm, and the areas near the surface have black rod-like and spherical particles, which are analyzed as SiO with different forms2Particles, the region close to the substrate being SiO in the form of flakes2The silicon steel decarburization oxide layer produced under the process condition has a good structure.
FIG. 2 is a photograph showing the morphology of grains in finished silicon steel in accordance with example 1 of the present invention. In the figure, the vertical direction is the Rolling Direction (RD) and the horizontal direction is the Transverse Direction (TD). As can be seen from FIG. 2, the grains of the product of example 1 have undergone good secondary recrystallization, and the size of the grains is relatively large, reaching the centimeter level and about 2-10 cm.
The present invention is not limited to the embodiments described above, but rather, the present invention can be implemented in other embodiments without departing from the scope of the present invention.
Claims (10)
1. B8The medium-temperature common oriented silicon steel with the temperature not less than 1.90T is characterized by comprising the following chemical components in percentage by weight: c: 0.020% -0.060%, Si: 2.80% -3.50%, Als: 0.010% -0.035%, N: 0.0060-0.0110%, Mn: 0.15% -0.30%, S: 0.0030% -0.0100%, Cu: 0.40 to 0.60 percent of the total weight of the alloy, less than or equal to 0.020 percent of P, V, Nb, B, Mo, Ti and Ca, less than or equal to 0.030 percent of (V + Nb + B + Mo + Ti + Ca), and the balance of iron and inevitable impurities.
2. The medium temperature normal orientation silicon steel of claim 1, wherein the medium temperature normal orientation silicon steel comprises the following chemical components in percentage by weight: c: 0.020% -0.060%, Si: 2.80% -3.50%, Als: 0.015% -0.030%, N: 0.0075-0.0090%, Mn: 0.19% -0.25%, S: 0.0050-0.0080%, Cu: 0.45 to 0.55 percent of the total weight of the alloy, less than or equal to 0.020 percent of P, V, Nb, B, Mo, Ti and Ca, less than or equal to 0.030 percent of (V + Nb + B + Mo + Ti + Ca), and the balance of iron and inevitable impurities.
3. A medium temperature ordinary oriented silicon steel as claimed in claim 1, wherein the medium temperature oriented silicon steel has a thickness of 0.23mm and a magnetic induction B8Not less than 1.90T, iron loss P1.7/50≤0.950W/kg。
4. A method for manufacturing medium temperature silicon steel for ordinary orientation according to any one of claims 1 to 3, wherein the method comprises the following steps:
1) smelting molten steel and continuously casting into a casting blank;
2) heating a casting blank to carry out hot rolling, wherein the heating temperature of the casting blank is 1250-1320 ℃; the finishing temperature is 900-1020 ℃, and the thickness of the hot rolled plate is 2.20-2.40 mm;
3) coiling, wherein the coiling temperature is controlled to be 500-600 ℃;
4) carrying out one-time cold rolling after conventional pickling, and controlling the rolling reduction rate to be 70-75%;
5) performing intermediate complete decarburization annealing and secondary cold rolling on the steel strip subjected to the cold rolling in the step (4), and controlling the reduction rate of the secondary cold rolling to be 60-65%; the decarburization annealing temperature is 790-860 ℃, the heat preservation time is 360s, and the protective atmosphere is H2And N2In the wet mixed gas of (2), wherein H2The volume content is 17-26%; the protective atmosphere is characterized in that the temperature of the water in the humidifier is adjusted to control the dew point of the atmosphere in the furnace to be 43-51 ℃;
6) coating an annealing release agent which takes MgO as a main component;
7) high-temperature purification annealing;
8) stretching, flattening, coating an insulating coating, and laser scoring to obtain B81.90T or more medium-temperature common oriented silicon steel.
5. The production method according to claim 4, wherein in the step (2), the temperature of heating the cast slab is 1250 to 1280 ℃.
6. The method according to claim 4, wherein in the step (5), the decarburization annealing is carried out at a temperature rise rate of 10 to 15 ℃/s to the decarburization annealing temperature.
7. The method according to claim 4, wherein in the step (5), the speed of the tapping cooling after the decarburization annealing of the steel strip is not less than 20 ℃/s.
8. The preparation method according to claim 4, wherein in the step (5), the temperature of the decarburization annealing is 800 to 850 ℃, and the holding time is 360 s; the protective atmosphere is H2And N2In the wet mixed gas of (2), wherein H2The volume content is 19-22%.
9. The preparation method of claim 4, wherein in the step (5), the specific process of controlling the water temperature of the humidifier comprises the following steps: controlling the water temperature of a humidifier to be 43-46 ℃ for 0-194 s of decarburization annealing; 194-284 s, and controlling the water temperature of the humidifier to be 46-49 ℃; 284-360 s, and controlling the water temperature of the humidifier to be 43-46 ℃.
10. The production method according to claim 4, wherein in the step (5), the oxygen content of the decarburization annealed steel strip is 700ppm or more and the carbon content is 25ppm or less.
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| CN1190132A (en) * | 1996-10-11 | 1998-08-12 | 川崎制铁株式会社 | Method for manufacturing high magnetic flux density oriented electric steel plate |
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| CN1190132A (en) * | 1996-10-11 | 1998-08-12 | 川崎制铁株式会社 | Method for manufacturing high magnetic flux density oriented electric steel plate |
| CN101492791A (en) * | 2008-01-24 | 2009-07-29 | 宝山钢铁股份有限公司 | Electromagnetic steel plate capable of soldering in large energy input and manufacturing method thereof |
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| EP2891728A1 (en) * | 2012-08-30 | 2015-07-08 | Baoshan Iron & Steel Co., Ltd. | High magnetic induction oriented silicon steel and manufacturing method thereof |
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