KR101633611B1 - High silicon electrical steel sheet with superior magnetic properties, and method for fabricating the high silicon electrical steel - Google Patents
High silicon electrical steel sheet with superior magnetic properties, and method for fabricating the high silicon electrical steel Download PDFInfo
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- KR101633611B1 KR101633611B1 KR1020140174452A KR20140174452A KR101633611B1 KR 101633611 B1 KR101633611 B1 KR 101633611B1 KR 1020140174452 A KR1020140174452 A KR 1020140174452A KR 20140174452 A KR20140174452 A KR 20140174452A KR 101633611 B1 KR101633611 B1 KR 101633611B1
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- 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
- C23C24/00—Coating starting from inorganic powder
- C23C24/02—Coating starting from inorganic powder by application of pressure only
- C23C24/04—Impact or kinetic deposition of particles
Abstract
A high silicon steel sheet excellent in magnetic properties and a method of manufacturing the same are provided. According to the present invention, there are provided a strip casting step of strip casting a silicon steel molten metal containing 4 to 7% of Si, 0.1 to 3% of Si, 5.5 to 7.5% of Si + Al and 5.5 to 7.5% of Si in weight ratio in a nitrogen or argon atmosphere A hot rolling step of hot stripping the strip cast strip to produce a high silicon steel sheet; a heat treatment step of heat treating the hot rolled high silicon steel sheet in a non-oxidizing atmosphere in a mixed atmosphere of nitrogen, argon or hydrogen and nitrogen; A hot rolling step of hot-rolling the heat-treated high silicon steel sheet to a final thickness of 0.5 mm or less and a final heat treatment step of subjecting the high silicon steel sheet to a final heat treatment at a temperature of 800 to 1200 占 폚 After the final heat treatment step is performed, a soft ferrite layer is formed on the surface of the high silicon steel sheet having a final thickness in order to improve the magnetism in the high frequency region And a system.
Description
The present invention relates to a high silicon steel sheet having excellent magnetic properties and a method of manufacturing the same. More specifically, the present invention relates to a high silicon steel sheet having magnetic properties And a method of manufacturing the same.
Generally, an electric steel sheet containing silicon is used as an iron core material for transformers, motors, generators, and other electronic devices. Electrical steel sheets are required to have excellent magnetic flux density and iron loss. The larger the magnetic flux density, the smaller the amount of iron core required to achieve the same performance, enabling the miniaturization of electrical equipment, and the smaller the core loss, the smaller the energy loss.
Iron loss, which causes energy loss, consists of eddy current loss and hysteresis loss. As the frequency increases in AC, the component of eddy current loss increases. The eddy current is generated by the eddy current generated when a magnetic field is induced in the iron core, so silicon is added to reduce the eddy current. When the silicon content is up to 6.5%, the magnetostriction, which causes noise, is reduced to zero and the permeability is at its maximum. In addition, when the silicon content is 6.5%, the high-frequency characteristics are greatly improved. It can be applied to the use of high value-added electric appliances such as inverters and reactors for new and renewable energy generation devices, generator induction heating devices for gas turbines, reactors of uninterruptible power supply devices, etc., by taking advantage of the excellent magnetic properties of such high silicon steel.
High silicon steel sheets containing 6.5% Si are excellent in magnetic properties, but can not be cold rolled by ordinary methods when the Si content exceeds 3.5%. Therefore, it is impossible to produce a high silicon steel sheet by ordinary hot rolling, cold rolling or warm rolling, so that it has been attempted to produce a high silicon steel sheet excellent in magnetic properties by other methods.
Techniques known to date for producing high silicon steel sheets include a direct casting method using a single-roll or twin-roll method such as Japanese Patent Laid-Open No. 56-3625, and Japanese Patent Application Laid-Open No. 5-171281, A so-called cladding method in which a low-silicon steel is rolled is attempted, but these techniques have not yet been commercialized.
Korean Patent Publication No. 10-0374292 discloses a powder metallurgy method in which a high-silicon steel block made of powder instead of a high silicon steel plate is formed and used as a substitute for silicon steel sheet. Pure iron powder cores, high-low-strength steel powder cores, and sandstop powder cores are used in combination, but their soft magnetic properties are lower than those of high-silicon steel sheets due to the characteristics of the powders.
Techniques for mass production of high silicon steel sheets containing 6.5% Si include Japanese Patent Publication No. 38-26263, which diffuses and anneals a 3% Si steel sheet using SiCl 4 by a chemical vapor deposition (CVD) method, Japan 45-21181, and Japanese Patent Laid-Open No. 62-227078. This method is disadvantageous in that a toxic SiCl 4 should be used and a long time is required for diffusion annealing.
As the silicon content in the electric steel sheet increases, the brittleness of the silicon steel sheet increases, and it is known that it is impossible to cold-roll a silicon steel sheet containing silicon of 3.5% Si or more. However, there has been an attempt to produce thin plates in an experimental manner by a so-called warm rolling method of increasing the rolling temperature.
Increasing the rolling temperature has an effect of improving the rolling property, but the improvement effect is not sufficient, and there are many difficulties in the process of manufacturing the hot rolled plate.
The present invention is to provide a high silicon steel sheet excellent in magnetic properties by remarkably improving the magnetism in a high frequency region by forming a MnZnNi soft ferrite layer having excellent high frequency characteristics on the surface of a high silicon steel sheet and a method of manufacturing the same.
According to one embodiment of the present invention, a silicon steel molten bath composed of 4 to 7% Si, 0.1 to 3% of Al, 5.5 to 7.5% of Si + Al and a balance of Fe is cast by strip casting in a nitrogen or argon atmosphere The hot-rolled high-silicon steel sheet is subjected to heat treatment in a non-oxidizing atmosphere in a mixed atmosphere of nitrogen, argon or hydrogen and nitrogen, and a hot-rolling step of hot-rolling the strip- A method of manufacturing a high silicon steel sheet, comprising: a heat treatment step; a warm rolling step of warm-rolling the heat-treated high silicon steel sheet to a final thickness of 0.5 mm or less; and a final heat treatment step of subjecting the high silicon steel sheet to a final heat treatment at a temperature of 800 to 1200 占 폚 In the production method of the present invention,
There is provided a method for manufacturing a high silicon steel sheet having excellent magnetic properties, comprising the steps of: forming a soft ferrite layer on a surface of a high silicon steel sheet having a final thickness in order to improve magnetism in a high frequency region after the final heat treatment step; .
The soft ferrite layer may be formed on both sides of the surface of the high silicon steel sheet produced to the final thickness.
The soft ferrite layer may be made of MnZnNi-based soft ferrite.
The MnZnNi-based soft ferrite may be composed of Mn oxide, Zn oxide, Ni oxide, and Fe oxide.
The sum of the both surface thicknesses of the soft ferrite layer may be 1 占 퐉 or more and 30 占 퐉 or less.
The soft ferrite layer forming step may include a step of mixing the soft ferrite powder with the surface of the high silicon steel plate,
Mixing the soft ferrite powder with a phosphate binder on the surface of the high silicon steel sheet, mixing the soft ferrite powder with an electric steel plate coating solution,
And a step of attaching the soft ferrite powder to the surface by colliding the soft ferrite powder with the steel sheet at a high speed in vacuum or at room temperature.
At least one or more of SiO 2 , CaO, Nb 2 O 5 , V 2 O 5 , ZrO 2 and MoO 3 may be added to the soft ferrite layer.
According to an embodiment of the present invention, there is provided a high silicon steel sheet excellent in magnetic properties, characterized in that a soft ferrite layer is formed on the surface of a high silicon steel sheet having a final thickness in order to improve magnetism in a high frequency region have.
The soft ferrite layer may be formed on both sides of the surface of the high silicon steel sheet produced to the final thickness.
The soft ferrite layer may be made of MnZnNi-based soft ferrite.
The MnZnNi-based soft ferrite may be composed of Mn oxide, Zn oxide, Ni oxide, and Fe oxide.
The sum of the both surface thicknesses of the soft ferrite layer may be 1 占 퐉 or more and 30 占 퐉 or less.
Wherein the soft ferrite layer is formed by mixing a soft ferrite powder with an electric steel plate coating liquid on the surface of the high silicon steel plate and applying the soft ferrite powder to the surface of the high silicon steel plate by mixing and coating the soft ferrite powder with a phosphate binder, A layer formed by mixing and coating an electric steel plate coating solution on the surface of the steel sheet, and a layer formed by attaching the soft ferrite powder to a surface of the steel sheet at a high speed in vacuum or at room temperature.
At least one or more of SiO 2 , CaO, Nb 2 O 5 , V 2 O 5 , ZrO 2 and MoO 3 may be added to the soft ferrite layer.
According to this embodiment, it is possible to manufacture a high silicon steel sheet in which the MnZnNi soft ferrite layer having excellent high frequency characteristics is formed on the surface of the high silicon steel sheet, thereby remarkably improving the magnetism in the high frequency region.
FIG. 1 is a configuration diagram of a method of manufacturing a high silicon steel sheet having excellent magnetic properties according to an embodiment of the present invention.
Hereinafter, embodiments of the present invention will be described with reference to the accompanying drawings so that those skilled in the art can easily carry out the present invention. It will be apparent to those skilled in the art that various modifications and variations can be made in the present invention without departing from the spirit or scope of the invention. Wherever possible, the same or similar parts are denoted using the same reference numerals in the drawings.
The terminology used herein is for the purpose of describing particular embodiments only and is not intended to limit the invention. The singular forms as used herein include plural forms as long as the phrases do not expressly express the opposite meaning thereto. Means that a particular feature, region, integer, step, operation, element and / or component is specified, and that other specific features, regions, integers, steps, operations, elements, components, and / And the like.
All terms including technical and scientific terms used herein have the same meaning as commonly understood by those of ordinary skill in the art to which the present invention belongs. Predefined terms are further interpreted as having a meaning consistent with the relevant technical literature and the present disclosure, and are not to be construed as ideal or very formal meanings unless defined otherwise.
The inventors of the present invention invented a method for producing a high silicon steel sheet by combining strip casting and warm rolling and substituting Al instead of 6.5% Si for excellent workability and excellent magnetic properties. This high silicon steel sheet has been developed to dramatically improve magnetic properties by forming a composite structure by forming this excellent soft ferrite powder layer.
Soft ferrite is a compound having a spinel-type crystal structure, in which the magnetic properties of the material are easily changed depending on the direction and the size of the magnetic field. Typically Fe2O3 iron oxide accounts for 60 to 70% by weight and is classified into manganese zinc ferrite, nickel zinc ferrite and magnesium zinc ferrite depending on the content of the remaining metal oxide. Hard ferrite, compared to soft ferrite, is a material in which the magnetic properties of a material do not change easily depending on the direction and magnitude of the magnetic field, and are generally referred to as permanent magnets. Fe2O3 iron oxide accounts for about 90% by weight and its application is divided according to the metal components added to improve other characteristics.
Generally, soft ferrite powders have high magnetic permeability and saturation magnetic flux density and have low magnetic deterioration at high temperature and excellent magnetic stability. In particular, MnZnNi ferrites have high saturation magnetic flux density, magnetic permeability and low loss magnetic properties in a relatively wide range of frequencies from 100 KHz to 500 KHz. Ferrite is used to make the core shape in sintered form of powder.
In the present invention, the method of forming these soft ferrite on the surface of the high silicon electrical steel sheet can remarkably improve the magnetism of the existing high silicon steel sheet. The high frequency characteristics of the high silicon steel sheet have excellent magnetic properties in the frequency range of several hundred Hz to several KHz. It has been found that the formation of a powdered soft ferrite layer having excellent high-frequency characteristics on the surface of such a high-silicon steel sheet results in further excellent characteristics.
When an electric steel sheet is used as a core, energy loss mainly occurs in the surface layer, and it is possible to remarkably improve iron loss by forming a soft ferrite layer having excellent high-frequency characteristics on the surface.
Hereinafter, a high silicon steel sheet having excellent magnetic properties according to an embodiment of the present invention will be described.
The high silicon steel sheet excellent in magnetic properties, particularly magnetic properties in a high frequency region according to an embodiment of the present invention, is characterized in that the steel containing a large amount of Si and Al in a content of not less than 5.5% is subjected to strip casting, hot rolling, , Hot rolling and the like to obtain a final thickness, and then a MnZnNi soft ferrite layer is formed on the surface.
Specifically, the high silicon steel sheet is subjected to strip casting in a nitrogen or argon atmosphere under a nitrogen or argon atmosphere in which the molten silicon steel comprising 4 to 7% of Si, 0.1 to 3% of Si, 5.5 to 7.5% of Si + Al, The strip-cast strip is hot-rolled to produce a high-silicon steel sheet. The hot-rolled high-silicon steel sheet is then heat-treated in a non-oxidizing atmosphere of nitrogen, argon or a mixed atmosphere of hydrogen and nitrogen, Hot-rolled, and then the high silicon steel sheet is subjected to final heat treatment at a temperature of 800 ° C to 1200 ° C,
A soft ferrite layer may be formed on the surface of the high silicon steel sheet having a final thickness to improve the magnetic properties in the high frequency region.
A method of manufacturing a high silicon steel sheet having excellent magnetic properties according to an embodiment of the present invention will be described.
A method of manufacturing a high silicon steel sheet having excellent magnetic properties according to an embodiment of the present invention comprises: 4 to 7% of Si, 0.1 to 3% of Al, 5.5 to 7.5% of Si + Al, A strip casting step (S10) of strip casting the silicon steel melt in a nitrogen or argon atmosphere,
A hot rolling step (S20) of hot-rolling the strip-cast strip to produce a high silicon steel sheet,
Thereafter, the hot-rolled high-silicon steel sheet is subjected to a heat treatment step (S30) for heat-treating the hot-rolled high-silicon steel sheet in a non-oxidizing atmosphere in a mixed atmosphere of nitrogen, argon or hydrogen and nitrogen,
Thereafter, the steel sheet is quenched to a temperature of 100 ° C at a cooling rate of 30 ° C / sec or more, and then subjected to warm rolling including at least one heat treatment at 900 to 1200 ° C, A warm rolling step (S40) of setting the high silicon steel sheet to a final thickness of 0.5 mm or less,
And a final heat treatment step (S50) of subjecting the high silicon steel sheet to a final heat treatment at a temperature of 800 to 1200 DEG C,
And a step (S60) of forming a soft ferrite layer on the surface of the high silicon steel sheet having a final thickness to improve the magnetic properties in the high frequency region after the final heat treatment step (S50).
It is not necessary to limit the method of manufacturing a high silicon steel sheet to a method of forming a soft ferrite layer on the surface layer of the high silicon steel sheet by a combination of strip casting and hot rolling. The present invention can be applied not only to rapid solidification by strip casting but also to processes that can be produced through steel-continuous casting-hot rolling. However, in a method other than strip casting, productivity may be extremely deteriorated due to occurrence of cracks during rolling. It is also applicable to a high silicon steel sheet produced by the method of Japanese Patent Application No. 38-26263, in which a high-gypsum steel is formed by a CVD method using a SiCl4 gas.
In the method for producing a high silicon steel sheet of the present invention, the lower the C content and the N content, the better the rolling property and the better the magnetism.
If the Si content is less than 4%, the magnetism is not good and if the Si content is 7% or more, processing is impossible.
If the Al content is 0.1% or less, the effect of improving the rolling property is not obtained. If the Al content is 3% or more, the rolling property is not good. When Si + Al is 5.5% or less, high-frequency characteristics are not good, and if it is 7.5% or more, processing is impossible.
Rather than hot rolling immediately after casting by strip casting, it is preferable to perform hot rolling immediately after strip casting, which can reduce the load of warm rolling. In addition, there is an advantage that hot strip rolling is directly connected to the strip casting production apparatus, and the strip is not heated separately. It is most preferable to hot-roll the strip immediately after casting, but it is preferable to cool the strip and then treat it in a separate line, rather than performing hot rolling immediately without hot rolling. In addition to reducing the load of hot rolling simply by hot rolling, hot rolling is performed to break down the casting structure to finely grind the crystal grains, which is helpful for warm rolling performed later.
It is preferable to heat-treat the hot-rolled plate rather than hot rolling it. Heat treatment is performed prior to hot rolling to eliminate the stress generated during hot rolling, and quenching after heat treatment in the A2 irregular phase region suppresses formation of B2 and DO3 regularity, thereby improving ductility.
According to the investigation on the hot rolling temperature, the critical temperature of 300 占 폚 was shown. When the temperature is lower than 300 ° C, the ductility hardly appears. If the temperature is higher than 300 ° C, the stretching is possible. At least 350 ° C is preferred for mass production.
The hot-rolled high-silicon steel sheet thinned to a final thickness of 0.5 mm or less is subjected to final heat treatment to improve the magnetic properties. When the heat treatment temperature is 800 DEG C or less, the grain growth is not sufficient and the iron loss is bad. If the heat treatment temperature is 1200 占 폚 or higher, it is not preferable from the viewpoint of economical efficiency and productivity, and even if a non-oxidizing atmosphere is used, the surface oxide layer tends to be formed, which hinders magnetism.
MnZnNi-based soft ferrite composed of manganese oxide, zinc oxide, nickel oxide and Fe-based oxide is applied to the surface of the high silicon steel having the final thickness. The soft ferrite powder may be mixed with a conventional electric steel plate coating liquid, or may be applied by mixing soft ferrite powder with a phosphate binder, and then applying a conventional electric steel plate coating liquid onto the soft ferrite powder.
The thickness of the soft ferrite layer made of the soft ferrite powder is set to 1 占 퐉 or more. If the thickness is 1 mu m or less, there is no effect of forming a composite structure. When the thickness of the soft ferrite layer is 30 占 퐉 or more, there is a disadvantage that the surface layer is broken when the steel sheet is hit, and the upper limit of the thickness is 30 占 퐉.
Demand for high-frequency electric steel sheets, which are used as iron core materials for high-frequency equipment, is increasing. Motor, dental power tool, motor of electric car, reactor, transformer for renewable energy, generator and so on. Typical high-frequency electric steel sheets are in the frequency range of several tens to several hundreds Hz, and the area covered by the high-grade steel is several hundred Hz to several KHz. On the other hand, powder sintered cores using soft ferrite are used at a frequency higher than several tens of kHz.
The present inventors continued research with the idea that if a soft ferrite layer is formed on the surface of a high silicon steel, not only the magnetism of the high frequency region which was responsible for high-frequency steel can be improved, but also the usable frequency region can be expanded, When a soft ferrite layer having a thickness of 1 탆 or more is formed on the surface of a silicon steel, the magnetism of the high silicon steel has been remarkably reduced. The soft ferrite layer is applied to both sides of the surface of the high silicon steel sheet in sheet form. The sum of the thicknesses of the soft ferrite layers applied on both surfaces of the surface of the high silicon steel sheet should be 1 탆 or more. However, it has been found that when the sum of both sides of the thickness of the soft ferrite layer exceeds 30 탆, the surface layer is crumbled when the steel sheet is punched into the core form, and it is difficult to maintain the surface layer.
Examples of the method for forming the soft ferrite layer include a method of mixing the soft ferrite powder with a conventional electric steel plate coating solution or a method of applying the soft ferrite powder to the high silicon steel plate in the form of a liquid mixed with a phosphate or a polymer, A method of applying the soft ferrite powder to a surface of a steel sheet at a high speed in a vacuum or a room temperature, and the like.
The structure of the soft ferrite layer is composed of so-called MnZnNi soft ferrite composed of manganese oxide, zinc oxide, nickel oxide and iron oxide. At least one or more of SiO 2 , CaO, Nb 2 O 5 , V 2 O 5 , ZrO 2 , and MoO 3 may be added to the soft ferrite. These oxides are excellent in magnetic properties in a high frequency range and can greatly improve the magnetic properties of the high silicon steel in the surface layer of the high silicon steel sheet.
In order to produce a core by sintering soft ferrite, the shape of the sintered body is different for each core, and there is a disadvantage in that a high-temperature high-pressure heat treatment is required in the production of cores. However, according to the present invention, it is advantageous to simply apply soft ferrite to the surface of a high silicon steel sheet having a small thickness, and to manufacture a core by assembling the steel sheet with a required size.
[Example 1]
A high-grade low-alloy steel having a composition of 5.5% Si and 1.0% Al by weight was cast to a thickness of 2.0 mm using a vertical twin-roll strip caster. The strip of 2.0 mm thickness was hot-rolled to 1.0 mm using a hot rolling mill connected to a strip caster. The hot rolling start temperature is 1050 占 폚.
The hot-rolled high silicon steel sheet was heated in an atmosphere of 20% hydrogen and 80% nitrogen at 1000 ° C for 5 minutes, and then quenched to room temperature at a cooling rate of 200 ° C / sec.
Thereafter, the surface oxide layer was removed by pickling with hydrochloric acid solution. The heat-treated high silicon steel sheet was annealed at a temperature of 400 DEG C to a thickness of 0.1 mm and then annealed at 1000 DEG C for 10 minutes in a dry atmosphere of hydrogen 20%, nitrogen 80%, dew point -10 DEG C or lower , MnZnNi soft ferrite was applied to the surface layer, the insulation coating was applied again on the coating layer, and then the magnetic property was measured by curing. The coating thickness is the sum of the upper and lower surfaces of the steel sheet. The composition and magnetic properties of soft ferrite are shown in Table 1 below.
[Table 1]
The B50 (T) in which the magnetic properties shown in Table 1 are measured is that the magnetic flux density is measured, and the higher the magnetic flux density, the better the magnetic properties are. In addition, W10 / 400 and W10 / 1000 were measured for iron loss at commercial frequency, and lower iron loss was evaluated as having lower magnetic property.
Here, B50 (T) is the magnetic flux density value in Telsa unit when the magnetic field strength is 5000 amp (amperes) / m, and W10 / 400 (W / Kg) is the frequency density when the magnetic flux density value is 1.0 Telsa. And W10 / 1000 (W / Kg) represents the iron loss value when the magnetic flux density is 1.0 Telsa and the frequency is 1000 Hz.
If the coating thickness of the soft ferrite layer is less than 1 탆, the high-frequency iron loss characteristic is poor and the soft ferrite coating effect is not obtained. If the applied thickness of the soft ferrite layer is 30 m or more, peeling of the soft ferrite layer of the surface layer occurs, and the surface roughness is not uniform, and the dot rate is decreased when the core is laminated.
S10: Strip casting Step S20: Hot rolling step
S30: heat treatment step S40: warm rolling step
S50: final heat treatment step
S60: Soft ferrite layer formation step
Claims (14)
Forming a soft ferrite layer on the surface of the high silicon steel sheet to a final thickness in order to improve the magnetism in the high frequency region after the final heat treatment step;
Lt; / RTI >
The soft ferrite layer forming step may include a step of mixing the soft ferrite powder with the surface of the high silicon steel plate,
Mixing the soft ferrite powder with a phosphate binder on the surface of the high silicon steel sheet, mixing the soft ferrite powder with an electric steel plate coating solution,
And the step of applying the soft ferrite powder to the surface of the steel sheet at a high speed in a vacuum or a room temperature and attaching the soft ferrite powder to the surface of the steel sheet.
Wherein the soft ferrite layer is formed on both sides of a surface of a high silicon steel sheet having a final thickness.
Wherein the soft ferrite layer is made of MnZnNi-based soft ferrite.
Wherein the MnZnNi-based soft ferrite is composed of Mn oxide, Zn oxide, Ni oxide and Fe oxide.
Wherein the sum of both thicknesses of the soft ferrite layer is 1 占 퐉 or more and 30 占 퐉 or less.
Wherein at least one of SiO 2 , CaO, Nb 2 O 5 , V 2 O 5 , ZrO 2 and MoO 3 is added to the soft ferrite layer.
A soft ferrite layer is formed on the surface of a high silicon steel sheet having a final thickness in order to improve the magnetic properties in a high frequency region,
Wherein the soft ferrite layer is formed by mixing a soft ferrite powder with an electric steel plate coating liquid on the surface of the high silicon steel plate and applying the soft ferrite powder to the surface of the high silicon steel plate by mixing and coating the soft ferrite powder with a phosphate binder, A layer formed by mixing and coating an electric steel sheet coating liquid on the surface of the steel sheet and a layer formed by bonding the soft ferrite powder to a surface of the steel sheet at a high speed in a vacuum or at room temperature and attaching the steel sheet to the surface thereof. Excellent high silicon steel sheet.
Wherein the soft ferrite layer is formed on both surfaces of a surface of a high silicon steel sheet having a final thickness.
Wherein the soft ferrite layer is made of MnZnNi soft ferrite.
Wherein the MnZnNi-based soft ferrite is composed of Mn oxide, Zn oxide, Ni oxide, and Fe oxide.
Wherein the soft ferrite layer has a total thickness of 1 占 퐉 or more and 30 占 퐉 or less.
Wherein at least one of SiO 2 , CaO, Nb 2 O 5 , V 2 O 5 , ZrO 2 and MoO 3 is added to the soft ferrite layer.
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| KR1020140174452A KR101633611B1 (en) | 2014-12-05 | 2014-12-05 | High silicon electrical steel sheet with superior magnetic properties, and method for fabricating the high silicon electrical steel |
| PCT/KR2015/012963 WO2016089076A1 (en) | 2014-12-05 | 2015-12-01 | High silicon steel plate having excellent magnetic property and manufacturing method thereof |
| CN201580066230.0A CN107002208B (en) | 2014-12-05 | 2015-12-01 | The excellent high silicon steel plate and preparation method thereof of magnetic property |
| JP2017529702A JP6523458B2 (en) | 2014-12-05 | 2015-12-01 | High silicon steel sheet excellent in magnetic property and method for producing the same |
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| JP6805978B2 (en) * | 2017-06-30 | 2020-12-23 | 日本製鉄株式会社 | Non-oriented electrical steel sheet and its manufacturing method |
| CN114293089B (en) * | 2021-12-31 | 2022-06-21 | 河北科技大学 | Soft magnetic high silicon steel ultra-thin strip and preparation method thereof |
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| JP2004197125A (en) * | 2002-12-16 | 2004-07-15 | Nippon Steel Corp | Magnetic ribbon superior in soft magnetic characteristic and manufacturing method therefor |
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| JPS61204909A (en) * | 1985-03-08 | 1986-09-11 | Pioneer Electronic Corp | Composite magnetic material |
| JPH07116513B2 (en) * | 1990-03-12 | 1995-12-13 | 日本鋼管株式会社 | Non-oriented electrical steel sheet manufacturing method |
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| JP2004197125A (en) * | 2002-12-16 | 2004-07-15 | Nippon Steel Corp | Magnetic ribbon superior in soft magnetic characteristic and manufacturing method therefor |
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| WO2016089076A1 (en) | 2016-06-09 |
| JP6523458B2 (en) | 2019-05-29 |
| CN107002208B (en) | 2018-12-11 |
| KR20160068563A (en) | 2016-06-15 |
| CN107002208A (en) | 2017-08-01 |
| JP2018504518A (en) | 2018-02-15 |
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