CN114622076A - Preparation method of low-temperature high-magnetic-induction oriented silicon steel - Google Patents
Preparation method of low-temperature high-magnetic-induction oriented silicon steel Download PDFInfo
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- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 24
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 238000005096 rolling process Methods 0.000 claims abstract description 82
- 238000000034 method Methods 0.000 claims abstract description 37
- 238000005098 hot rolling Methods 0.000 claims abstract description 23
- 238000010438 heat treatment Methods 0.000 claims abstract description 21
- 238000005097 cold rolling Methods 0.000 claims abstract description 19
- 238000003723 Smelting Methods 0.000 claims abstract description 16
- 238000000137 annealing Methods 0.000 claims abstract description 15
- 238000005266 casting Methods 0.000 claims abstract description 14
- 238000005261 decarburization Methods 0.000 claims abstract description 14
- 238000010606 normalization Methods 0.000 claims abstract description 11
- 239000002994 raw material Substances 0.000 claims abstract description 8
- 238000005121 nitriding Methods 0.000 claims description 16
- 239000012298 atmosphere Substances 0.000 claims description 14
- 230000008569 process Effects 0.000 claims description 10
- 238000001816 cooling Methods 0.000 claims description 9
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 claims description 8
- 239000000463 material Substances 0.000 claims description 8
- 230000009467 reduction Effects 0.000 claims description 7
- 239000011248 coating agent Substances 0.000 claims description 5
- 238000000576 coating method Methods 0.000 claims description 5
- 238000003825 pressing Methods 0.000 claims description 5
- 230000032683 aging Effects 0.000 claims description 4
- 229910021529 ammonia Inorganic materials 0.000 claims description 4
- 238000000354 decomposition reaction Methods 0.000 claims description 4
- 230000002441 reversible effect Effects 0.000 claims description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 238000007599 discharging Methods 0.000 claims description 2
- 229910000831 Steel Inorganic materials 0.000 abstract description 10
- 239000010959 steel Substances 0.000 abstract description 10
- 238000001953 recrystallisation Methods 0.000 abstract description 8
- 239000013078 crystal Substances 0.000 abstract description 6
- 230000006698 induction Effects 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 18
- 229910052742 iron Inorganic materials 0.000 description 9
- 229910000805 Pig iron Inorganic materials 0.000 description 5
- 239000010410 layer Substances 0.000 description 4
- 238000004321 preservation Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000012299 nitrogen atmosphere Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 239000003112 inhibitor Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
- B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/58—Roll-force control; Roll-gap control
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
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- C—CHEMISTRY; METALLURGY
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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
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
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Abstract
The invention discloses a preparation method of low-temperature high-magnetic induction oriented silicon steel, which comprises the steps of smelting raw materials to form a first blank; continuously casting the first blank to form a second blank, wherein the thickness of the casting blank is 200-250 mm; heating the second blank; hot rolling the heated blank II; hot rolling is carried out by adopting a rolling mill; normalizing the pressed blank II to form a blank III; cold rolling the blank III by adopting a 20-roller reversing mill; carrying out decarburization and nitridation processing on the cold-rolled blank III to form a blank IV; carrying out high-temperature annealing operation on the blank IV to form a blank V; the method is suitable for the technical field of steel smelting, and can flatten and deform the crystal grains after hot rolling through first cold rolling with proper deformation, reduce the recrystallization temperature during normalization, obtain more and more uniform crystal grains after normalization, increase the size of the crystal grains and be more accurate after primary recrystallization in decarburization annealing.
Description
Technical Field
The invention relates to the technical field of steel smelting, in particular to a preparation method of low-temperature high-magnetic-induction oriented silicon steel.
Background
Iron and steel smelting is a general term for steel and iron metallurgical technological processes. The iron produced in industry is divided into pig iron according to the carbon content, and the carbon content is more than 2%; steel, with a carbon content of less than 2%.
Most of modern iron making adopts blast furnace iron making, and a direct reduction iron making method and an electric furnace iron making method are respectively adopted. The steel-making is mainly made by using pig iron smelted by blast furnace, sponge iron smelted by direct reduction iron-smelting method and waste steel as raw materials and smelting into steel by different methods. The basic production process is that iron ore is smelted into pig iron in an iron-smelting furnace, then the pig iron is used as raw material, and the pig iron is smelted into steel by different methods and then is casted into steel ingots or continuous casting billets.
The low-temperature high-magnetic-induction oriented silicon steel is prepared by smelting, and the conventional process of the low-temperature high-magnetic-induction oriented silicon steel comprises the following steps: smelting, continuous casting, heating a plate blank at 1150-1200 ℃, hot rolling to the specification of 2.2-2.5 mm, normalizing, cold rolling to the specification of 0.27mm, decarbonizing and nitriding, high-temperature annealing and flattening and stretching.
The following problems mainly exist in the conventional process production:
(1) and because the heating temperature of the plate blank is low and the rolling specification is thin, the finish rolling temperature can only be controlled to be 880-920 ℃ generally, and because the peak precipitation temperature of AlN is about 950 ℃, the C-class AlN with the precipitation of more than 100nm at high temperature in the hot rolling process is increased. Causing the reduction of B-class AlN of a size of 20-100 nm of the effective inhibitor after normalization;
(2) the hot rolling is carried out until the standard is 2.2-2.5 mm, a common continuous rolling unit has certain rolling difficulty, rolling from a thicker standard is often required, then the target standard is gradually transited, and the transition coil cannot be continuously used and is discarded. Meanwhile, the temperature is low, the specification is thin, the rolling stability is poor, and the plate shape problem is easy to occur and scrap;
(3) in the hot rolling, the surface layer grains are recrystallized to form equiaxed grains, and the other parts are basically deformed grains, so that the hot rolling two-phase grains are unevenly precipitated due to the nonuniformity of grain boundary distribution. After normalization, the grain nonuniformity after grain recrystallization is easily increased, strip breakage is easily caused in the subsequent cold rolling process, and meanwhile, a deformation strip formed in the cold rolling process is uniformly reduced, so that the grain nonuniformity of primary recrystallization and secondary recrystallization is influenced, and the magnetic performance is finally reduced.
Disclosure of Invention
The invention aims to provide a preparation method of low-temperature high-magnetic-induction oriented silicon steel, which aims to solve the problems in the background technology.
In order to achieve the purpose, the invention provides the following technical scheme:
a preparation method of low-temperature high-magnetic-induction oriented silicon steel comprises the following steps:
the method comprises the following steps: smelting the raw materials to form a first blank;
step two: continuously casting the first blank to form a second blank, wherein the thickness of the casting blank is 200-250 mm;
step three: heating the second blank;
step four: hot rolling the heated blank II;
step five: the hot rolling is carried out by adopting a rolling mill for pressing, a reversible rolling mill or a continuous rolling mill is adopted for carrying out cold rolling for 1-5 times to reach the specification of 2.2-2.5 mm, and the deformation is 30-60%;
step six: normalizing the pressed blank II to form a blank III;
step seven: cold rolling the blank III by adopting a 20-roller reversing mill;
step eight: carrying out decarburization and nitridation processing on the cold-rolled blank III to form a blank IV;
step nine: carrying out high-temperature annealing operation on the blank IV to form a blank V;
step ten: and (4) flatly stretching the blank five, cooling, coating an insulating layer, stretching and flatly stretching to finally form the low-temperature high-magnetic-induction oriented silicon steel.
As a further scheme of the invention, the heating temperature in the third step is 1160-1200 ℃, the heating time is 200-300 min, wherein the heating time above 1100 ℃ is 100-150 min.
According to a further scheme of the invention, the hot rolling in the fourth step is divided into rough rolling and finish rolling, wherein the initial rolling temperature of the rough rolling is 1080-1150 ℃, and the final rolling temperature of the rough rolling is 1060-1080 ℃; the initial rolling temperature of finish rolling is 1050-1070 ℃, the final rolling temperature of finish rolling is controlled to be 940-980 ℃, the coiling temperature is controlled to be 520-560 ℃, the specification of a hot rolling material is controlled to be 3.5-5 mm, and the deformation of a rough rolling pass is 25-35%.
As a further scheme of the invention, the total deformation of rough rolling is 75-85%, and the thickness after rough rolling is 45 mm; the deformation of the finish rolling pass is 15-50%, and the total deformation of the finish rolling is 85-95%.
According to a further scheme of the invention, the normalization in the sixth step adopts a two-stage normalization process, wherein the temperature of the high-temperature stage is 1050-1090 ℃, the temperature is kept for 40-70 s, then the temperature is reduced to 870-920 ℃, and the temperature reduction rate is 15-20 ℃/s; and preserving heat for 100-150 s at a low-temperature section, and then discharging from the furnace, and then cooling by water at a cooling speed of 40-60 ℃/s.
As a further scheme of the invention, in the seventh step, the total cold rolling deformation is controlled to be 87-90%, the pass deformation is controlled from large to small in sequence, and the aging rolling temperature is controlled to be 200-250 ℃.
As a further scheme of the invention, in the step eight, the temperature rise speed of decarburization in decarburization and nitridation is controlled to be 20-50 ℃/s, the annealing temperature is 820-860 ℃, and the annealing time is controlled to be 2.5-3.5 min.
As a further scheme of the invention, in the ninth step, the high-temperature annealing is carried out at full speed under the atmosphere of N2 to raise the temperature to 650-750 ℃, then the temperature is maintained for 18-25 hours under the atmosphere of N2 with the volume fraction of 50% and H2 with the volume fraction of 50%, then the temperature is raised to 1200 ℃ under the atmosphere of ammonia decomposition gas at the temperature raising rate of 17-25 ℃/H, and then the temperature is maintained for 25 hours under the atmosphere of pure H2.
According to a further scheme of the invention, in the step eight, the decarburization and nitridation are performed by adopting two-stage nitridation, wherein the nitridation temperature of the first stage is 850-900 ℃, and the nitridation temperature of the second stage is 780-800 ℃.
As a further scheme of the invention, in the step ten, the flattening and the stretching are operated by a flattening machine and a stretching machine.
Compared with the prior art, the invention has the following beneficial effects:
(1) the first cold rolling with proper deformation can flatten and deform the crystal grains after hot rolling, the recrystallization temperature is reduced during normalization, more and more uniform crystal grains can be obtained after normalization, the size of the crystal grains is larger, and the primary recrystallization in decarburization annealing can be more accurate.
(2) The hot rolling specification is thicker, the temperature drop is smaller, the finish rolling temperature is higher during hot rolling, and C-class AlN precipitated at high temperature can be effectively reduced by more than 100nm, so that the quantity of B-class AlN precipitated at high temperature is increased by 20-100 nm after normalization;
(3) the temperature difference between the head and the tail is effectively reduced, and the nonuniformity of the roll passing is reduced;
(4) the material loss caused by poor transition materials and plate shapes is effectively reduced;
(5) after the primary cold rolling, the thickness of the steel strip is uniform, and the accurate control of secondary cold rolling deformation can be realized;
(6) and the increase of the deformation amount of the two-time cold rolling promotes the homogenization development of the primary recrystallization.
Drawings
The invention is further illustrated with reference to the following figures and examples.
FIG. 1 is a schematic view of a flow frame of a preparation method of the low-temperature high-magnetic-induction oriented silicon steel of the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention. In addition, for the convenience of description, the following references to "upper", "lower", "left" and "right" are to be construed as referring to the upper, lower, left, right, etc. direction of the attached drawings, and the following references to "first", "second", etc. are to be distinguished for descriptive purposes and not for other specific meanings.
The preparation method of the low-temperature high-magnetic-induction oriented silicon steel comprises the following steps:
the method comprises the following steps: smelting the raw materials to form a first blank;
step two: continuously casting the first blank to form a second blank, wherein the thickness of the casting blank is 200-250 mm;
step three: heating the second blank;
step four: hot rolling the heated blank II;
step five: the hot rolling is carried out by adopting a rolling mill for pressing, a reversible rolling mill or a continuous rolling mill is adopted for carrying out cold rolling for 1-5 times to reach the specification of 2.2-2.5 mm, and the deformation is 30-60%;
step six: normalizing the pressed blank II to form a blank III;
step seven: cold rolling the blank III by using a 20-roller reversible rolling mill;
step eight: carrying out decarburization and nitridation processing on the cold-rolled blank III to form a blank IV;
step nine: carrying out high-temperature annealing operation on the blank IV to form a blank V;
step ten: and (4) flatly stretching the blank five, cooling, coating an insulating layer, stretching and flatly stretching to finally form the low-temperature high-magnetic-induction oriented silicon steel.
[ example 1 ]
Firstly, the method comprises the following steps: smelting the raw materials;
II, secondly: continuously casting after smelting, wherein the thickness of a casting blank is 200-250 mm;
thirdly, the steps of: hot charging the casting blank at 500 ℃, wherein the heating temperature is 1185 ℃, the heating time is 235min, and the heating time above 1100 ℃ is 115 min;
fourthly, the method comprises the following steps: then, hot rolling is carried out, the initial rolling temperature of rough rolling is 1125 ℃, the final rolling temperature of rough rolling is 1069 ℃, the pass deformation of rough rolling is 25-35%, the total deformation of rough rolling is 75-85%, and the thickness after rough rolling is 45 mm; the initial rolling temperature of finish rolling is 1060 ℃, the final rolling temperature of finish rolling is controlled to be 965 ℃, the coiling temperature is controlled to be 520-560 ℃, the deformation of a finish rolling pass is 15-50%, the total deformation of finish rolling is 85.3%, and the specification of a hot rolled material is controlled to be 3.95 mm;
fifthly: pressing by a rolling mill, and cold-rolling to 2.25mm specification by a continuous rolling unit for 5 times;
sixthly, the method comprises the following steps: adopting a two-stage normalizing process, wherein the heat preservation temperature of a normalizing high-temperature section is 1080 ℃, the temperature is preserved for 50s and then is reduced to 890 ℃, the temperature reduction rate is 18 ℃/s, the temperature is preserved for 120s and then the material is taken out of the furnace and then is cooled by water, and the cooling speed is 48 ℃/s;
seventhly, the method comprises the following steps: the total deformation is controlled to be 88.9 percent, the pass deformation is controlled from large to small in sequence, and the aging rolling temperature is controlled to be 150-250 ℃;
eighthly: the heating rate is 30 ℃/s, the heat preservation temperature of the decarburization section is 830 ℃, and the annealing time is controlled at 185 s; nitriding by adopting two-stage nitriding, wherein the nitriding temperature of the first stage is 860 ℃, the nitriding temperature of the second stage is 800 ℃, and the average nitriding amount is 239 ppm;
nine: raising the temperature to 730 ℃ at full speed in an N2 atmosphere, then preserving the temperature for 20 hours in an atmosphere of N2 with the volume fraction of 50% and H2 with the volume fraction of 50%, then raising the temperature to 1200 ℃ at the temperature raising rate of 19 ℃/H in an ammonia decomposition gas atmosphere, and then preserving the temperature for 25 hours in a pure H2 atmosphere;
ten: coating an insulating layer and stretching to be flat.
[ example 2 ]
Firstly, the method comprises the following steps: smelting the raw materials;
II, secondly: continuously casting after smelting, wherein the thickness of a casting blank is 200-250 mm;
thirdly, the method comprises the following steps: hot charging the casting blank at 600 ℃, wherein the heating temperature is 1185 ℃, the heating time is 235min, and the heating time above 1100 ℃ is 115 min;
fourthly, the method comprises the following steps: then, hot rolling is carried out, the initial rolling temperature of rough rolling is 1135 ℃, the final rolling temperature of rough rolling is 1072 ℃, the deformation of the rough rolling pass is 25-35%, the total deformation of the rough rolling is 75-85%, and the thickness after the rough rolling is 45 mm; the initial rolling temperature of finish rolling is 1065 ℃, the finish rolling temperature of finish rolling is controlled to be 963 ℃, and the coiling temperature is controlled to be 520-560 ℃; the deformation of the finish rolling pass is 15-50%, the total deformation of the finish rolling is 85.4%, and the specification of the hot rolled material is controlled to be 4.30 mm;
fifthly: pressing by a rolling mill, and cold-rolling to 2.25mm specification by a continuous rolling unit for 5 times;
sixthly, the method comprises the following steps: adopting a two-stage normalizing process, wherein the heat preservation temperature of a normalizing high-temperature section is 1080 ℃, the temperature is preserved for 50s and then is reduced to 890 ℃, the temperature reduction rate is 18 ℃/s, the temperature is preserved for 120s and then the material is taken out of the furnace and then is cooled by water, and the cooling speed is 48 ℃/s;
seventhly, the method comprises the following steps: the total deformation is controlled to be 88.9 percent, the pass deformation is controlled from large to small in sequence, and the aging rolling temperature is controlled to be 150-250 ℃;
eighthly: the heating rate is 30 ℃/s, the heat preservation temperature of the decarburization section is 830 ℃, and the annealing time is controlled at 185 s; nitriding by adopting two-stage nitriding, wherein the nitriding temperature of the first stage is 860 ℃, the nitriding temperature of the second stage is 800 ℃, and the average nitriding amount is 239 ppm;
nine: raising the temperature to 730 ℃ at full speed in an N2 atmosphere, then preserving the temperature for 20 hours in an atmosphere of N2 with the volume fraction of 50% and H2 with the volume fraction of 50%, then raising the temperature to 1200 ℃ at the temperature raising rate of 19 ℃/H in an ammonia decomposition gas atmosphere, and then preserving the temperature for 25 hours in a pure H2 atmosphere;
ten: coating an insulating layer and stretching to be flat.
From the above, it can be seen that:
the yield of the first example was 85.3%, P1.7 was 0.96W/kg, and B8 was 1.93;
the yield of example two was 85.4%, P1.7 was 0.97W/kg, and B8 was 1.93.
The above description is only for the purpose of illustrating the preferred embodiments of the present invention and is not to be construed as limiting the invention, and any modifications, equivalents and improvements made within the spirit and principle of the present invention are intended to be included within the scope of the present invention.
Claims (10)
1. A preparation method of low-temperature high-magnetic-induction oriented silicon steel is characterized by comprising the following steps: the preparation method of the low-temperature high-magnetic-induction oriented silicon steel comprises the following steps:
the method comprises the following steps: smelting the raw materials to form a first blank;
step two: continuously casting the first blank to form a second blank, wherein the thickness of the casting blank is 200-250 mm;
step three: heating the second blank;
step four: hot rolling the heated blank II;
step five: the hot rolling is carried out by adopting a rolling mill for pressing, a reversible rolling mill or a continuous rolling mill is adopted for carrying out cold rolling for 1-5 times to reach the specification of 2.2-2.5 mm, and the deformation is 30-60%;
step six: normalizing the pressed blank II to form a blank III;
step seven: cold rolling the blank III by adopting a 20-roller reversing mill;
step eight: carrying out decarburization and nitridation processing on the cold-rolled blank III to form a blank IV;
step nine: carrying out high-temperature annealing operation on the blank IV to form a blank V;
step ten: and (4) flatly stretching the blank five, cooling, coating an insulating layer, stretching and flatly stretching to finally form the low-temperature high-magnetic-induction oriented silicon steel.
2. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: the heating temperature in the third step is 1160-1200 ℃, the heating time is 200-300 min, and the heating time above 1100 ℃ is 100-150 min.
3. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: the hot rolling in the fourth step comprises rough rolling and finish rolling, wherein the initial rolling temperature of the rough rolling is 1080-1150 ℃, and the final rolling temperature of the rough rolling is 1060-1080 ℃; the initial rolling temperature of the finish rolling is 1050-1070 ℃, the final rolling temperature of the finish rolling is controlled to be 940-980 ℃, the coiling temperature is controlled to be 520-560 ℃, the specification of the hot rolling material is controlled to be 3.5-5 mm, and the deformation of the rough rolling pass is 25-35%.
4. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 3, characterized by comprising the following steps: the total deformation of the rough rolling is 75-85%, and the thickness after the rough rolling is 45 mm; the deformation of the finish rolling pass is 15-50%, and the total deformation of the finish rolling is 85-95%.
5. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: the normalization in the sixth step adopts a two-stage normalization process, wherein the temperature of the high-temperature stage is 1050-1090 ℃, the temperature is kept for 40-70 s, then the temperature is reduced to 870-920 ℃, and the temperature reduction rate is 15-20 ℃/s; and preserving heat for 100-150 s at a low-temperature section, and then discharging from the furnace, and then cooling by water at a cooling speed of 40-60 ℃/s.
6. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: and in the seventh step, the total cold rolling deformation is controlled to be 87-90%, the pass deformation is controlled from large to small in sequence, and the aging rolling temperature is controlled to be 200-250 ℃.
7. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: and step eight, controlling the temperature rise speed of decarburization in decarburization and nitridation to be 20-50 ℃/s, adopting the annealing temperature of 820-860 ℃ and controlling the annealing time to be 2.5-3.5 min.
8. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: in the ninth step, the high-temperature annealing is carried out, the temperature is raised to 650-750 ℃ at full speed under the atmosphere of N2, then the heat is preserved for 18-25 hours under the atmosphere of N2 with the volume fraction of 50% and H2 with the volume fraction of 50%, then the temperature is raised to 1200 ℃ under the atmosphere of ammonia decomposition gas at the heating rate of 17-25 ℃/H, and then the heat is preserved for 25 hours under the atmosphere of pure H2.
9. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: and eighthly, nitriding in the decarburization and nitriding process adopts two-section nitriding, wherein the nitriding temperature of the first section is 850-900 ℃, and the nitriding temperature of the second section is 780-800 ℃.
10. The method for preparing low-temperature high-magnetic-induction oriented silicon steel according to claim 1, characterized by comprising the following steps: and in the step ten, flattening and stretching are performed by adopting a flattening machine and a stretching machine.
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