CN110318005B - High magnetic induction oriented silicon steel and manufacturing method thereof - Google Patents
High magnetic induction oriented silicon steel and manufacturing method thereof Download PDFInfo
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
Abstract
The invention discloses high magnetic induction oriented silicon steel which comprises the following chemical elements in percentage by mass: 0.035-0.120% of C, 2.5-4.5% of Si, 0.05-0.20% of Mn, 0.005-0.05% of P, 0.005-0.012% of S, 0.015-0.035% of Als, 0.002-0.1% of Bi, 0.003-0.010% of N, 0.05-0.30% of Cr, 0.03-0.30% of Sn, 0.01-0.50% of Cu and the balance of Fe and inevitable impurities. The invention also discloses a manufacturing method of the high-magnetic-induction oriented silicon steel, which comprises the following steps: (1) smelting and casting; (2) heating a casting blank; (3) hot rolling: the initial rolling temperature is less than or equal to 1200 ℃, the final rolling temperature is more than or equal to 900 ℃, and after rolling, laminar cooling is carried out, wherein the coiling temperature is less than or equal to 650 ℃; (4) normalizing and annealing: heating to 1100-1120 ℃ at the speed of 5-10 ℃/s, keeping the temperature for less than or equal to 60s, cooling to 930-960 ℃ within the time of less than or equal to 15s, keeping the temperature for 120-250 s, and performing water quenching at the cooling speed of 10-100 ℃/s; (5) cold rolling; (6) decarburization annealing and nitriding treatment; (7) coating a MgO coating, drying and annealing, and then annealing at high temperature; (8) and coating an insulating coating, and carrying out hot stretching flattening annealing to obtain the high-magnetic-induction oriented silicon steel coil.
Description
Technical Field
The invention relates to oriented silicon steel and a manufacturing method thereof, in particular to high magnetic induction oriented silicon steel and a manufacturing method thereof.
Background
The traditional high magnetic induction oriented silicon steel has two main processes: high temperature processes and low temperature processes. The traditional high-temperature process takes MnS + AIN as an inhibitor and adopts a normalizing and one-time cold rolling process for production. The production process is characterized in that the heating temperature of the plate blank is as high as 1400 ℃ in the hot rolling process so that MnS and AlN in the steel plate are fully dissolved in a solid mode, and are separated out in the subsequent normalizing process by fine and dispersed second phase particles, so that the second phase particles are used as an inhibitor for primary crystal grain growth, and the secondary recrystallization process of high-temperature annealing is promoted to form Gaussian crystal grains with larger sizes so as to obtain the high-magnetic-induction oriented silicon steel product with high orientation degree and low iron loss. However, the heating of the high-temperature plate blank has the defects of low yield, serious slag deposition at the bottom of the furnace, low yield, high energy consumption, short service life of the furnace, high manufacturing cost, more defects on the surface of the product and unstable magnetic property. The traditional low-temperature process can reduce the heating temperature of the plate blank to 1150 ℃, only trace Al element is added during steel making, and nitriding treatment is carried out after decarburization and annealing. The process is mainly characterized in that during low-temperature heating in the decarburization annealing process, as coarse sulfides and nitrides cannot be dissolved in a solid manner, an inhibitor cannot be formed in hot rolling and normalizing, but an inhibitor AlN is formed in a nitrifiable atmosphere after the decarburization annealing. However, in the low temperature process, since AlN cannot be completely dissolved in a solid solution during the heating stage of decarburization annealing, the amount of inhibitor is insufficient, and secondary recrystallization cannot sufficiently occur, and therefore, it is necessary to find a method for enhancing the effect of the inhibitor in order to improve the magnetic properties of the oriented silicon steel.
In the prior art, most researches are focused on obtaining oriented silicon steel with excellent magnetic performance under high-temperature process conditions, a small amount of oriented silicon steel with good magnetic performance under low-temperature process conditions is involved, and mature process technologies are not formed yet.
In view of the above, it is desirable to obtain a high magnetic induction grain-oriented silicon steel, the composition of which is designed to enhance the inhibitor effect, so that the final product has high magnetic induction and stable magnetic performance, and the manufacturing method of which can widen the process windows of normalizing annealing and decarburization annealing.
Disclosure of Invention
One of the objects of the present invention is to provide a high magnetic induction oriented silicon steel having high magnetic induction and stable magnetic properties.
In order to achieve the purpose, the invention provides high magnetic induction oriented silicon steel which comprises the following chemical elements in percentage by mass:
0.035-0.120% of C, 2.5-4.5% of Si, 0.05-0.20% of Mn, 0.005-0.05% of P, 0.005-0.012% of S, 0.015-0.035% of Als, 0.002-0.1% of Bi, 0.003-0.010% of N, 0.05-0.30% of Cr, 0.03-0.30% of Sn, 0.01-0.50% of Cu and the balance of Fe and inevitable impurities.
The design principle of each chemical element in the high magnetic induction grain-oriented silicon steel is as follows:
c: c mainly has the function of leading the steel to contain 20 to 30 percent of gamma phase in the hot rolling process
Phase transformation refines the hot rolled plate structure, and the hot rolled plate structure presents a specific structure gradient along the plate thickness direction, namely the center of the plate has fine grain structure due to high C content; in the vicinity of the plate surface, the amount of C is small due to decarburization, and ferrite grains are coarse, and coarse and accurately oriented Gaussian grains are easily formed in the rolling direction. The invention limits the content of C in the high magnetic induction grain-oriented silicon steel to be within the range of 0.035-0.120%.
Si: the inventor of the present invention found out through research that the iron loss P of the steel is increased by 0.1% Si17/50The flow rate is reduced by 0.019W/kg. However, too high Si content causes rapid decrease in γ phase content, difficulty in material processing, coarsening of the hot-rolled sheet structure, coarsening and reduction in the number of precipitated inhibitors, reduction in the inhibitory power of the inhibitors, coarsening of primary recrystallized grains, reduction in the (110) pole density in the primary recrystallized structure, and difficulty in secondary recrystallization.In addition, too high Si content results in coarse carbide particles precipitated after normalization, which affects cold rolling aging and decarburization annealing. Therefore, the Si content in the high magnetic induction grain-oriented silicon steel is controlled to be 2.5-4.5%.
Mn: on one hand, the main function of Mn is to prevent hot-rolled plates from being hot-brittle, Mn can form MnS precipitates with S, primary recrystallization grains are fine and uniform, and secondary recrystallization development is promoted; on the other hand, Mn expands the gamma phase region, reduces the C content, and reduces the burden of decarburization in the subsequent step. However, when the Mn content is too high, a gamma phase appears in the subsequent step, and the secondary recrystallization process is disturbed. Therefore, the Mn content in the high magnetic induction grain-oriented silicon steel is controlled to be 0.05-0.20%.
P: p can promote primary recrystallization to be fine and uniform, and meanwhile, the components of {111} texture in primary crystal grains are improved, and secondary recrystallization is perfected. However, the steel is embrittled when the P content is too high, so the P content in the high magnetic induction grain-oriented silicon steel is controlled to be 0.005-0.05%.
S: the inventors of the present invention found through studies that when S is less than 0.005%, not only steel making is difficult, but also magnetic properties are affected because AlN and (Cu, Mn) S have a certain orientation relationship: (2110) AlN// (110) (Cu, Mn) S, too high or too low of S content affects the AlN precipitation morphology. When S is more than 0.012%, secondary recrystallization is incomplete and wire crystals are likely to occur. Therefore, the S content in the high-magnetic-induction oriented silicon steel is controlled to be 0.005-0.012%.
Als (acid-soluble aluminum) and N: AlN is a main inhibitor in the oriented silicon steel, and in order to ensure the magnetism of steel, the content of Als in the high-magnetic-induction oriented silicon steel is limited to 0.015-0.035%, and the content of N is limited to 0.003-0.010%.
Bi: bi is a low-melting-point metal element which is segregated along a grain boundary, is mostly compositely precipitated with AlN and MnS precipitated in a hot plate blank and is distributed in a dispersed bubble shape or liquid state in steel, so that the number of fine and dispersed impurities in the hot plate blank is increased, the effect of inhibiting primary grain growth is enhanced, the size of secondary recrystallization grains of a finished product is increased, and the stability and the improvement of magnetic performance are facilitated. In addition, along with the increase of Bi content, the inhibition effect on the growth of crystal grains is enhanced when the decarburization annealing plate is heated, so that the starting temperature of secondary recrystallization is increased, namely, only Gaussian crystal nuclei with more accurate positions can grow up and obtain a size effect to swallow the crystal grains with other positions, and the finally obtained steel plate has better magnetism. Meanwhile, as the content of Bi increases, the number of secondary grains decreases and the size of the secondary grains increases, so that the magnetic properties can be improved.
In addition, the inventor of the present invention finds, through research, that adding a trace amount of Bi in steel can widen the window of the post-process normalizing annealing and decarburization annealing process, make the influence of the key process on magnetism less sensitive, and thus can improve the toughness of the normalized steel plate and make the steel plate more convenient for cold rolling. Further, the inventors of the present invention have found, through studies, that when Bi is added to steel, the suppression capability is improved, and the cold rolling reduction is improved, thereby improving the magnetic properties. Meanwhile, the decarburization temperature can be widened, so that the final finished product has stable magnetic property and high magnetic induction, and the yield of the oriented silicon steel is improved. Therefore, it is very important to control the Bi element, and when the Bi content is less than 0.002%, there is no effect on the improvement of magnetic properties, and when the Bi content is more than 0.1%, the underlayer property is deteriorated. Therefore, the Bi content in the high magnetic induction oriented silicon steel is limited to 0.002% -0.1%.
Cr: the addition of Cr can promote the oxidation during decarburization annealing, improve the oxygen adhesion amount and improve the bottom layer quality, so the Cr content in the high magnetic induction grain-oriented silicon steel is controlled to be 0.05-0.30 percent.
Sn: sn is a grain boundary segregation element, and the addition of Sn can strengthen the inhibiting effect and prevent premature N removal and N increase in the high-temperature annealing process, thereby promoting the perfection of secondary recrystallization and improving the magnetism. However, Sn occupies the grain boundary, and inhibits the diffusion of O, which affects the formation of the underlying damascene structure, and deteriorates the quality of the underlying layer. The Sn content in the high magnetic induction grain-oriented silicon steel is controlled to be 0.03-0.30%.
Cu: cu can increase the content of gamma phase, properly reduce the content of C and reduce the burden of decarburization in the subsequent process. After Cu is added, (Cu, Mn) xS or CuxS particles can be precipitated, which are more finely dispersed particles than MnS, so that the inhibition force can be enhanced, and the magnetism of the finished product can be improved. Further, the addition of Cu improves (110) <001> orientation grains after hot-rolled sheet and decarburization annealing, reduces {100} <001> orientation grains, promotes secondary recrystallization, and improves the effect of glass film deterioration due to Sn addition. However, the Cu content is too high, which not only increases the cost, but also causes the gamma phase in the subsequent process, which interferes the secondary recrystallization process. Therefore, the Cu content in the high magnetic induction grain-oriented silicon steel is controlled to be 0.01-0.50%.
Furthermore, the high magnetic induction grain-oriented silicon steel also contains at least one of V which is more than 0 and less than or equal to 0.0100 percent and Ti which is more than 0 and less than or equal to 0.0100 percent.
In the technical scheme, V, Ti is a strong carbide forming element, and the decarburization annealing process is influenced when the content of the element is high, so that the control is required, the content of V in the high magnetic induction oriented silicon steel is limited to be more than 0 and less than or equal to 0.0100 percent, and the content of Ti in the high magnetic induction oriented silicon steel is limited to be more than 0 and less than or equal to 0.0100 percent.
Furthermore, in the high magnetic induction oriented silicon steel of the invention, the magnetic induction B8Not less than 1.95T, iron loss P17/50≤0.93W/kg。
Furthermore, in the high magnetic induction oriented silicon steel, the secondary grain size is 28-32 mm.
Accordingly, another object of the present invention is to provide a method for manufacturing the above-mentioned high magnetic induction oriented silicon steel, which includes reasonable component design and optimized process design, so that the manufactured high magnetic induction oriented silicon steel has high magnetic induction and stable magnetic performance. Meanwhile, the manufacturing method can widen the process windows of normalizing annealing and decarburization annealing.
In order to achieve the purpose, the invention provides a method for manufacturing high magnetic induction oriented silicon steel, which comprises the following steps:
(1) smelting and casting;
(2) heating a casting blank;
(3) hot rolling: controlling the initial rolling temperature to be less than or equal to 1200 ℃, controlling the final rolling temperature to be more than or equal to 900 ℃, performing laminar cooling after rolling, and controlling the coiling temperature to be less than or equal to 650 ℃ so as to separate out fine and dispersed impurities in the hot rolled plate;
(4) normalizing and annealing: heating to 1100-1120 ℃ at the speed of 5-10 ℃/s, keeping the temperature for less than or equal to 60s, cooling to 930-960 ℃ within the time of less than or equal to 15s, keeping the temperature for 120-250 s, and performing water quenching at the cooling speed of 10-100 ℃/s;
(5) cold rolling;
(6) decarburization annealing and nitriding treatment;
(7) coating a MgO coating, carrying out drying annealing, and then carrying out high-temperature annealing;
(8) and coating an insulating coating, and carrying out hot stretching flattening annealing to obtain the high-magnetic-induction oriented silicon steel coil.
In the above-described manufacturing method, in step (1), in some embodiments, the molten steel may be subjected to smelting in a converter or an electric furnace, and secondary refining and continuous casting may be performed on the molten steel to obtain a cast slab. In step (4), the hot-rolled sheet is subjected to normalization annealing in order to precipitate a fine AlN inhibitor, increase the number of recrystallized grains of the hot-rolled sheet, and make the texture distribution more reasonable. In step (5), in some embodiments, the cold rolling process may include an intermediate anneal. The specific process of the intermediate annealing is a conventional process in the prior art, and is not described herein again. In step (6), in some embodiments, a nitriding treatment is performed during the decarburization annealing process or at a later stage. The purpose of the nitriding is to form favorable inclusions, and after the nitriding is completed, nitrogen penetrating into the surface of the steel sheet will diffuse and form favorable inclusions mainly of (Al, Si) N, which act to suppress the growth of primary grains and prepare for the occurrence of secondary recrystallization. In step (7), in some embodiments, a hood-type furnace or a ring furnace may be used for the dry annealing and/or the high temperature annealing.
Further, in the manufacturing method of the present invention, in the step (1), the degree of superheat of the molten steel is controlled to be 5 to 25 ℃, and the casting speed is controlled to be 0.5 to 2.0 m/min.
Furthermore, in the manufacturing method of the present invention, in the step (2), the heating temperature is controlled to be 1130 to 1330 ℃, and the heating time is controlled to be 150 to 600 min.
In the manufacturing method of the invention, in the step (2), the heating temperature is controlled to be 1130-1330 ℃, and the heating time is controlled to be 150-600 min. This is because: on the one hand, in order to ensure the stability of hot working, precipitates formed in the casting process are dissolved in the matrix again in a solid manner, and the heating temperature of a casting blank cannot be too low; on the other hand, the heating temperature of the cast slab cannot be too high in order to prevent deterioration of magnetic properties, oxidation burning and edge cracking. In addition, the inhibitor and (Cu, Mn) S with lower solid solution temperature are formed by adopting a decarburization annealing back-stage nitriding method, so that the heating temperature is controlled to be 1130-1330 ℃, and the heating time is controlled to be 150-600 min.
Further, in the production method of the present invention, in the step (5), the total rolling reduction is controlled to be not less than 85%.
In the manufacturing method of the invention, in the step (5), the cold rolling deformation and the inhibiting capability of the inhibitor of the oriented silicon steel have a matching relationship, and the cold rolling under high pressure can be realized only by strong inhibiting capability. The invention adds Bi element to enhance the inhibiting capability, so that the invention adopts large reduction ratio cold rolling with total reduction ratio more than or equal to 85 percent to form more {111} <112> deformation zones, transition zones composed of (110) [001] subgrains with high energy storage are arranged between the deformation zones, and the (110) [001] subgrains are aggregated to form (110) [001] Gaussian crystal nuclei with more accurate orientation during subsequent annealing, thereby improving the magnetism.
Further, in the manufacturing method of the present invention, in the step (6), two-stage decarburization annealing is performed, wherein in the first stage, the decarburization annealing temperature is controlled to be 800 to 900 ℃, the decarburization annealing time is controlled to be 80 to 160s, and the partial pressure ratio pH of the decarburization annealing atmosphere is controlled to be pH2O/pH20.4 to 0.75; wherein the temperature of decarburization annealing is controlled to be 800-950 ℃ in the second stage, the time of decarburization annealing is controlled to be 40-60 s, and the partial pressure ratio pH of decarburization annealing atmosphere is controlled to be2O/pH2<0.4。
In the manufacturing method of the invention, the two-stage decarburization annealing is carried out in the step (6), which can ensure full decarburization, improve the quality of the glass film, ensure the stability of secondary recrystallization and ensure that secondary crystal grains are small, thereby improving the magnetism.
Further, in the manufacturing method of the present invention, in the step (6), the nitriding temperature of the nitriding treatment is 750 to 900 ℃, the nitriding time is 5 to 50s, and the nitriding atmosphere is NH3+H2+N2Wherein NH3The volume percentage of the nitrogen-containing material is 0.1-15%, and the nitriding amount is 50-250 ppm.
Further, in the manufacturing method of the present invention, in the dry annealing step of the step (7): in N2+H2Heating to 550-650 ℃ at a speed of 10-50 ℃/h in the atmosphere, and keeping the temperature for a period of time to remove crystal water in MgO; in the high temperature annealing step: heating to 900-1100 ℃ at a speed of 15-20 ℃/h; then heating to 1200 +/-20 ℃ at the speed of 10-20 ℃/H, and heating to 100% of H2Preserving the heat for 15-20 h in the atmosphere, and then cooling to 500-650 ℃ at the speed of 120-150 ℃/h.
In the high temperature annealing step of the above-mentioned manufacturing method step (7), in some embodiments, after cooling the steel sheet to 500 to 650 ℃, it is then annealed at 100% N2Furnace cooling is carried out in the atmosphere.
Compared with the prior art, the high magnetic induction oriented silicon steel and the manufacturing method thereof have the following beneficial effects:
(1) the high-magnetic-induction oriented silicon steel disclosed by the invention has the advantages that through reasonable component design, the number of fine dispersed inclusions precipitated in a hot rolled plate is increased, so that the action of an inhibitor is strengthened, the magnetic performance of the high-magnetic-induction oriented silicon steel is improved, and the magnetic induction B is8Not less than 1.95T, iron loss P17/50≤0.93W/kg。
(2) Compared with the traditional manufacturing method, the manufacturing method of the high magnetic induction oriented silicon steel can widen the normalizing annealing temperature by 50-150 ℃, widen the decarburization annealing temperature by 20-40 ℃, and improve the cold rolling reduction rate to more than 85%.
Drawings
Fig. 1 is a microstructure diagram showing the morphology and distribution of Bi precipitates in a hot slab of high magnetic induction grain-oriented silicon steel in example 2 of the present invention.
Fig. 2 is a morphological-component surface scanning diagram of Bi precipitates in a hot slab of high magnetic induction grain-oriented silicon steel in example 2 of the present invention.
FIG. 3 is a diagram showing the secondary recrystallized structure of high magnetic induction grain-oriented silicon steel in example 4 of the present invention.
Detailed Description
The high magnetic induction grain-oriented silicon steel and the method for manufacturing the same according to the present invention will be further explained and illustrated with reference to the accompanying drawings and specific examples, which, however, should not be construed as unduly limiting the technical scope of the invention.
Examples 1 to 9 and comparative examples 1 to 6
Tables 1 to 1 and tables 1 to 2 show the mass percentages of the chemical elements in the high magnetic induction grain-oriented silicon steels of examples 1 to 9 and comparative examples 1 to 6.
TABLE 1-1. (wt.%, balance Fe and unavoidable impurities)
| Serial number | C | Si | Mn | S | Cr | Als | N |
| Example 1 | 0.051 | 3.24 | 0.099 | 0.0087 | 0.15 | 0.0267 | 0.0086 |
| Example 2 | 0.064 | 3.19 | 0.15 | 0.0070 | 0.20 | 0.028 | 0.008 |
| Example 3 | 0.053 | 3.22 | 0.098 | 0.0079 | 0.11 | 0.027 | 0.0079 |
| Example 4 | 0.052 | 3.22 | 0.11 | 0.0068 | 0.13 | 0.0294 | 0.0081 |
| Example 5 | 0.083 | 3.45 | 0.098 | 0.009 | 0.25 | 0.029 | 0.009 |
| Example 6 | 0.055 | 3.35 | 0.10 | 0.0093 | 0.11 | 0.0272 | 0.0087 |
| Example 7 | 0.094 | 2.95 | 0.08 | 0.008 | 0.08 | 0.031 | 0.0075 |
| Example 8 | 0.056 | 3.30 | 0.12 | 0.0065 | 0.095 | 0.033 | 0.0092 |
| Example 9 | 0.051 | 3.17 | 0.11 | 0.0065 | 0.11 | 0.0269 | 0.0077 |
| Comparative example 1 | 0.062 | 3.20 | 0.11 | 0.0062 | 0.11 | 0.0268 | 0.0077 |
| Comparative example 2 | 0.053 | 3.27 | 0.13 | 0.0077 | 0.13 | 0.0269 | 0.0079 |
| Comparative example 3 | 0.055 | 3.28 | 0.089 | 0.0068 | 0.11 | 0.0275 | 0.0077 |
| Comparative example 4 | 0.060 | 3.20 | 0.11 | 0.0062 | 0.14 | 0.0268 | 0.0078 |
| Comparative example 5 | 0.054 | 3.17 | 0.13 | 0.0077 | 0.13 | 0.0269 | 0.0079 |
| Comparative example 6 | 0.055 | 3.22 | 0.092 | 0.0070 | 0.10 | 0.0275 | 0.0077 |
Tables 1-2 (wt%, balance Fe and inevitable impurities)
| Serial number | Sn | Cu | V | Ti | Bi | P |
| Example 1 | 0.047 | 0.3 | 0.0006 | 0.0012 | 0.020 | 0.05 |
| Example 2 | 0.067 | 0.01 | 0.0008 | 0.0021 | 0.025 | 0.026 |
| Example 3 | 0.046 | 0.05 | 0.0012 | 0.0012 | 0.031 | 0.028 |
| Example 4 | 0.047 | 0.15 | 0.0007 | 0.0012 | 0.044 | 0.045 |
| Example 5 | 0.09 | 0.3 | 0.0009 | 0.0013 | 0.053 | 0.005 |
| Example 6 | 0.05 | 0.25 | 0.0009 | 0.0012 | 0.062 | 0.025 |
| Example 7 | 0.083 | 0.03 | 0.0012 | 0.0025 | 0.075 | 0.027 |
| Example 8 | 0.055 | 0.20 | 0.0007 | 0.0028 | 0.083 | 0.038 |
| Example 9 | 0.048 | 0.04 | 0.0012 | 0.0021 | 0.098 | 0.027 |
| Comparative example 1 | 0.049 | 0.05 | 0.002 | 0.0016 | 0.0005 | 0.027 |
| Comparative example 2 | 0.052 | 0.02 | 0.0007 | 0.0022 | 0.0005 | 0.026 |
| Comparative example 3 | 0.047 | 0.02 | 0.002 | 0.0024 | 0.0005 | 0.030 |
| Comparative example 4 | 0.049 | 0.04 | 0.003 | 0.0016 | 0.0005 | 0.015 |
| Comparative example 5 | 0.052 | 0.01 | 0.0009 | 0.0026 | 0.0005 | 0.043 |
| Comparative example 6 | 0.047 | 0.03 | 0.003 | 0.0023 | 0.0005 | 0.035 |
The high magnetic induction grain-oriented silicon steels of examples 1 to 9 and comparative examples 1 to 6 were prepared by the following steps:
(1) smelting and casting: proportioning the chemical elements in the mass percentages in the tables 1-1 and 1-2, smelting by adopting a converter or an electric furnace, performing secondary refining and continuous casting on the molten steel to obtain a casting blank, controlling the superheat degree of the molten steel to be 5-25 ℃ and the casting speed to be 0.5-2.0 m/min;
(2) heating a casting blank: controlling the heating temperature to be 1130-1330 ℃, and the heating time to be 150-600 min;
(3) hot rolling: controlling the initial rolling temperature to be less than or equal to 1200 ℃, controlling the final rolling temperature to be more than or equal to 900 ℃, performing laminar cooling after rolling, and controlling the coiling temperature to be less than or equal to 650 ℃ to obtain a hot rolled plate with the thickness of 2-4 mm;
(4) normalizing and annealing: heating to 1100-1120 ℃ at the speed of 5-10 ℃/s, keeping the temperature for less than or equal to 60s, cooling to 930-960 ℃ within the time of less than or equal to 15s, keeping the temperature for 120-250 s, and performing water quenching at the cooling speed of 30-100 ℃/s;
(5) cold rolling: controlling the total reduction rate to be 85-92%, and rolling the steel plate to the thickness of the finished plate substrate;
(6) decarburization annealing and nitriding treatment: performing two-stage decarburization annealing, wherein the decarburization annealing temperature is controlled to be 800-900 ℃ in the first stage, the decarburization annealing time is 80-160 s, and the partial pressure ratio pH of the decarburization annealing atmosphere is controlled to be2O/pH20.4 to 0.75; wherein the temperature of decarburization annealing is controlled to be 800-950 ℃ in the second section, the time of decarburization annealing is controlled to be 40-60 s, and the partial pressure ratio pH of decarburization annealing atmosphere is controlled to be2O/pH2<0.4. Nitriding treatment is carried out after decarburization annealing, the nitriding temperature of the nitriding treatment is controlled to be 750-900 ℃, the nitriding time is controlled to be 5-50 s, and the nitriding atmosphere is NH3+H2+N2Wherein NH3The volume percentage of the nitrogen-containing material is 0.1-15%, and the nitriding amount is 50-250 ppm;
(7) coating MgO coating, then carrying out drying annealing in a bell type furnace or an annular furnace, and then carrying out high-temperature annealing. Wherein, in the dry annealing step: in N2+H2Heating to 550-650 ℃ at a speed of 10-50 ℃/h in the atmosphere, and preserving heat for a period of time; in the high temperature annealing step: heating to 900-1100 ℃ at a speed of 15-20 ℃/h; then heating to 1200 +/-20 ℃ at the speed of 10-20 ℃/H, and heating to 100% of H2Keeping the temperature for 15-20H in the atmosphere, and then keeping the temperature at 100% H2Cooling the steel plate to 500-650 ℃ at a speed of 120-150 ℃/h in the atmosphere, and then adding 100% N2Furnace cooling is carried out in the atmosphere;
(8) and coating an insulating coating after uncoiling, and performing hot stretching, flattening and annealing to obtain the finished high-magnetic-induction oriented silicon steel coil.
Tables 2-1, 2-2, 2-3, 2-4, and 2-5 show the specific process parameters of the methods for manufacturing high magnetic induction grain-oriented silicon steels of examples 1-9 and comparative examples 1-6.
Table 2-1.
Table 2-2.
Tables 2 to 3.
Tables 2 to 4.
Tables 2 to 5.
The high magnetic induction grain-oriented silicon steels of examples 1 to 9 and comparative examples 1 to 6 were subjected to magnetic property test, and the iron loss P17/50And magnetic induction B8The test results of (2) are shown in Table 3.
Table 3.
As can be seen from FIGS. 1 to 3, in example 2, Bi low-melting point metal (the melting point thereof is 271 ℃) is added in the steel-making process, the atomic radius is larger than that of Fe, the Bi low-melting point metal is extremely difficult to dissolve in Fe, the Bi low-melting point metal is deviated along grain boundaries, the Bi low-melting point metal is distributed in a dispersed bubble shape (as shown in FIG. 1) or a liquid state (as shown in FIG. 2) in the steel, and precipitates such as AlN are wrapped. Example 4 since Bi inhibits the movement of grain boundaries, retards the decomposition of the inhibitor, and thus inhibits the growth of primary grains, the temperature at which secondary recrystallization starts is increased, i.e., only those gaussian nuclei with more precise orientation can grow and obtain a size effect to engulf grains with other orientations, and thus the secondary recrystallized grain size of the final product can be increased to 28-32mm (see fig. 3), which is beneficial to the stabilization and improvement of magnetic properties.
It should be noted that the prior art in the protection scope of the present invention is not limited to the examples given in the present application, and all the prior art which is not inconsistent with the technical scheme of the present invention, including but not limited to the prior patent documents, the prior publications and the like, can be included in the protection scope of the present invention.
In addition, the combination of the features in the present application is not limited to the combination described in the claims of the present application or the combination described in the embodiments, and all the features described in the present application may be freely combined or combined in any manner unless contradictory to each other.
It should also be noted that the above-mentioned embodiments are only specific embodiments of the present invention. It is apparent that the present invention is not limited to the above embodiments and similar changes or modifications can be easily made by those skilled in the art from the disclosure of the present invention and shall fall within the scope of the present invention.
Claims (9)
1. The high magnetic induction oriented silicon steel is characterized by comprising the following chemical elements in percentage by mass:
0.035-0.120% of C, 2.5-4.5% of Si, 0.05-0.20% of Mn, 0.005-0.05% of P, 0.005-0.012% of S, 0.015-0.035% of Als, 0.031-0.1% of Bi, 0.003-0.010% of N, 0.05-0.30% of Cr, 0.03-0.30% of Sn, 0.01-0.50% of Cu and the balance of Fe and inevitable impurities;
wherein the secondary grain size of the high magnetic induction grain-oriented silicon steel is 28-32 mm.
2. The high magnetic induction grain-oriented silicon steel as claimed in claim 1, further comprising at least one of 0 < V.ltoreq.0.0100% and 0 < Ti.ltoreq.0.0100%.
3. The high magnetic induction grain-oriented silicon steel of claim 1, wherein the magnetic induction B is8Not less than 1.95T, iron loss P17/50≤0.93W/kg。
4. The method of manufacturing high magnetic induction grain-oriented silicon steel as claimed in any one of claims 1 to 3, comprising the steps of:
(1) smelting and casting;
(2) heating a casting blank: controlling the heating temperature to be 1130-1250 ℃ and the heating time to be 150-600 min;
(3) hot rolling: controlling the initial rolling temperature to be less than or equal to 1200 ℃, controlling the final rolling temperature to be more than or equal to 900 ℃, performing laminar cooling after rolling, and controlling the coiling temperature to be less than or equal to 650 ℃ so as to separate out fine and dispersed impurities in the hot rolled plate;
(4) normalizing and annealing: heating to 1100-1120 ℃ at the speed of 5-10 ℃/s, keeping the temperature for less than or equal to 60s, cooling to 930-960 ℃ within the time of less than or equal to 15s, keeping the temperature for 120-250 s, and performing water quenching at the cooling speed of 10-100 ℃/s;
(5) cold rolling;
(6) decarburization annealing and nitriding treatment;
(7) coating a MgO coating, carrying out drying annealing, and then carrying out high-temperature annealing;
(8) and coating an insulating coating, and carrying out hot stretching flattening annealing to obtain the high-magnetic-induction oriented silicon steel coil.
5. The method according to claim 4, wherein in the step (1), the degree of superheat of the molten steel is controlled to be 5 to 25 ℃ and the casting speed is controlled to be 0.5 to 2.0 m/min.
6. The production method according to claim 4, wherein in the step (5), the total rolling reduction is controlled to be 85% or more.
7. The method according to claim 4, wherein in the step (6), two-stage decarburization annealing is performed, wherein the decarburization annealing temperature is controlled to 800 to 900 ℃ in the first stage, the decarburization annealing time is controlled to 80 to 160 seconds, and the partial pressure ratio of the atmosphere of the decarburization annealing is adjusted to pH2O/pH20.4 to 0.75; wherein the temperature of decarburization annealing is controlled to be 800-950 ℃ in the second stage, the time of decarburization annealing is controlled to be 40-60 s, and the partial pressure ratio pH of decarburization annealing atmosphere is controlled to be2O/pH2<0.4。
8. The method according to claim 4, wherein in the step (6), the nitriding temperature of the nitriding treatment is 750 to 900 ℃, the nitriding time is 5 to 50s, and the nitriding atmosphere is NH3+H2+N2Wherein NH3The volume percentage of the nitrogen-containing material is 0.1-15%, and the nitriding amount is 50-250 ppm.
9. The manufacturing method according to claim 4, wherein in the dry annealing step of the step (7): in N2+H2Heating to 550-650 ℃ at a speed of 10-50 ℃/h in the atmosphere, and keeping the temperature for a period of time to remove crystal water in MgO; in the high temperature annealing step: heating to 900-1100 ℃ at a speed of 15-20 ℃/h; then heating to 1200 +/-20 ℃ at the speed of 10-20 ℃/H, and heating to 100% of H2Preserving the heat for 15-20 h in the atmosphere, and then cooling to 500-650 ℃ at the speed of 120-150 ℃/h.
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Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000199014A (en) * | 1998-12-28 | 2000-07-18 | Kawasaki Steel Corp | Production of grain oriented silicon steel sheet |
| CN102787276A (en) * | 2012-08-30 | 2012-11-21 | 宝山钢铁股份有限公司 | High magnetic induction oriented silicon steel and manufacturing method thereof |
| CN103668005A (en) * | 2013-12-12 | 2014-03-26 | 武汉钢铁(集团)公司 | HiB steel produced at moderate slab heating temperature and production method thereof |
| CN103667874A (en) * | 2013-05-20 | 2014-03-26 | 新万鑫（福建）精密薄板有限公司 | Production method for shortening furnace time of oriented silicon steel during high-temperature annealing period |
| CN103695791A (en) * | 2013-12-11 | 2014-04-02 | 武汉钢铁(集团)公司 | High-magnetic strength oriented silicon steel and production method thereof |
| CN103805918A (en) * | 2012-11-15 | 2014-05-21 | 宝山钢铁股份有限公司 | High-magnetic induction oriented silicon steel and production method thereof |
| CN104870665A (en) * | 2012-12-28 | 2015-08-26 | 杰富意钢铁株式会社 | Production method for grain-oriented electrical steel sheet and primary recrystallized steel sheet for production of grain-oriented electrical steel sheet |
| JP2017222898A (en) * | 2016-06-14 | 2017-12-21 | 新日鐵住金株式会社 | Production method of grain oriented magnetic steel sheet |
| CN107746942A (en) * | 2017-12-15 | 2018-03-02 | 武汉钢铁有限公司 | A kind of B800 >=1.962T low temperature superelevation magnetic induction grain-oriented silicon steel and production method |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7399369B2 (en) * | 2001-07-16 | 2008-07-15 | Nippon Steel Corporation | Ultra-high magnetic flux density grain-oriented electrical steel sheet excellent in iron loss at a high magnetic flux density and film properties and method for producing the same |
| CN103834856B (en) * | 2012-11-26 | 2016-06-29 | 宝山钢铁股份有限公司 | Orientation silicon steel and manufacture method thereof |
| CN103911545A (en) * | 2014-04-14 | 2014-07-09 | 国家电网公司 | Preparation method of electrical steel strip with strong goss texture occupation rate and high magnetic induction orientation |
-
2018
- 2018-03-30 CN CN201810286833.7A patent/CN110318005B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000199014A (en) * | 1998-12-28 | 2000-07-18 | Kawasaki Steel Corp | Production of grain oriented silicon steel sheet |
| CN102787276A (en) * | 2012-08-30 | 2012-11-21 | 宝山钢铁股份有限公司 | High magnetic induction oriented silicon steel and manufacturing method thereof |
| CN103805918A (en) * | 2012-11-15 | 2014-05-21 | 宝山钢铁股份有限公司 | High-magnetic induction oriented silicon steel and production method thereof |
| CN104870665A (en) * | 2012-12-28 | 2015-08-26 | 杰富意钢铁株式会社 | Production method for grain-oriented electrical steel sheet and primary recrystallized steel sheet for production of grain-oriented electrical steel sheet |
| CN103667874A (en) * | 2013-05-20 | 2014-03-26 | 新万鑫（福建）精密薄板有限公司 | Production method for shortening furnace time of oriented silicon steel during high-temperature annealing period |
| CN103695791A (en) * | 2013-12-11 | 2014-04-02 | 武汉钢铁(集团)公司 | High-magnetic strength oriented silicon steel and production method thereof |
| CN103668005A (en) * | 2013-12-12 | 2014-03-26 | 武汉钢铁(集团)公司 | HiB steel produced at moderate slab heating temperature and production method thereof |
| JP2017222898A (en) * | 2016-06-14 | 2017-12-21 | 新日鐵住金株式会社 | Production method of grain oriented magnetic steel sheet |
| CN107746942A (en) * | 2017-12-15 | 2018-03-02 | 武汉钢铁有限公司 | A kind of B800 >=1.962T low temperature superelevation magnetic induction grain-oriented silicon steel and production method |
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