KR20150073799A - Oriented electrical steel sheet and method for manufacturing the same - Google Patents
Oriented electrical steel sheet and method for manufacturing the same Download PDFInfo
- Publication number
- KR20150073799A KR20150073799A KR1020130161899A KR20130161899A KR20150073799A KR 20150073799 A KR20150073799 A KR 20150073799A KR 1020130161899 A KR1020130161899 A KR 1020130161899A KR 20130161899 A KR20130161899 A KR 20130161899A KR 20150073799 A KR20150073799 A KR 20150073799A
- Authority
- KR
- South Korea
- Prior art keywords
- steel sheet
- annealing
- hot
- slab
- aluminum
- Prior art date
Links
Classifications
-
- 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
-
- 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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Power Engineering (AREA)
- Dispersion Chemistry (AREA)
- Electromagnetism (AREA)
- Manufacturing & Machinery (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
The present invention relates to a directional electrical steel sheet and a method of manufacturing the same, and more particularly, to a directional electrical steel sheet having improved magnetic properties and iron loss by controlling a component system and a method of manufacturing the same.
The oriented electrical steel sheet has a so-called Goss texture in which the orientation of all the grains on the steel sheet face is {110} plane and the crystal orientation in the rolling direction is parallel to the <001> axis, This is a very good soft magnetic material.
In the case of grain-oriented electrical steel sheet, the resistivity value of the electrical steel sheet should be high and the grain size should be appropriately controlled in order to obtain good iron loss. If the inherent resistance is low, the eddy current loss becomes large, and the iron loss becomes worse.
Conventionally, alloying elements such as Si, Al, and Mn have been mainly added to increase the resistivity.
However, the addition of such an alloying element causes a problem that the material is hardened when the material is added in a large amount, and the content of the impurity element is increased due to the use of a large amount of the alloying element.
SUMMARY OF THE INVENTION The present invention has been made to solve the above problems, and it is an object of the present invention to provide a directional electric steel sheet having an increased aluminum content in a steel sheet and having low iron loss and excellent magnetic properties.
A method for manufacturing a grain-oriented electrical steel sheet according to the present invention comprises: 2.0 to 6.5% of Si, 0.040% or less of Al (not including 0%), 0.20% or less of Mn (not including 0% 0.01% or less (not including 0%), S: 0.01% or less (excluding 0%), P: 0.005 to 0.05%, C: 0.04 to 0.12% Providing a slab comprising impurities to be incorporated; Reheating the slab; Hot-rolling the slab to produce a hot-rolled steel sheet; Cold-rolling the hot-rolled steel sheet to produce a cold-rolled steel sheet; Subjecting the cold-rolled steel sheet to decarburization annealing and steep annealing; And a step of hot-dipping aluminum molten metal on the electric steel sheet after the decarburization annealing and the steep annealing have been completed; Applying an annealing separator to perform final annealing; .
The step of performing the hot dip coating may be a method of producing a directional electrical steel sheet in which an aluminum-silicon molten metal is hot-dip coated.
The hot-dip coating temperature in the hot-dip coating step may be 600 to 900 ° C.
In the step of reheating the slab, the total amount of nitrogen reused in the slab may be 20 to 50 ppm.
In the step of reheating the slab, the reheating temperature may be a temperature range in which the dissolved N and S are incompletely dissolved, and the temperature range in which the incomplete melting can be performed may be 1250 ° C or less.
Further comprising the step of annealing the hot-rolled steel sheet after the hot-rolling, wherein the average size of the precipitates in the steel sheet after annealing the hot-rolled sheet may be 200 to 3000 Å.
The step of producing the cold-rolled steel sheet can be rolled at a rate of 87% or more by one-time cold rolling.
The decarburization annealing and the steep annealing can be performed at 800 to 950 ° C.
The final annealing may be performed in a mixed atmosphere of nitrogen and hydrogen gas at a temperature rising period before the secondary recrystallization, and in a hydrogen atmosphere after completion of secondary recrystallization.
The step of performing the decarburization annealing and the steep annealing of the cold-rolled steel sheet may be performed simultaneously with the decarburization annealing and the steep annealing.
The grain-oriented electrical steel sheet according to one embodiment of the present invention contains 2.0 to 6.5% of Si, 0.040% or less of Al (does not include 0%), 0.20% or less of Mn (does not include 0% ), N: not more than 0.01% (not including 0%), S: not more than 0.01% (not including 0%), P: 0.005 to 0.05%, C: 0.04 to 0.12% , And aluminum is a hot-dip galvanized steel sheet.
The electrical steel sheet may be a directional electrical steel sheet in which aluminum-silicon is hot-dip coated.
The grain-oriented electrical steel sheet according to another embodiment of the present invention comprises 2.0 to 6.5% of Si, 0.040% or less of Al (not including 0%), 0.20% or less of Mn 0.01% or less (not including 0%), S: 0.01% or less (not including 0%), P: 0.005 to 0.05%, C: 0.04 to 0.12% After the slab containing Fe and other inevitably impurities is heated, hot-rolled, cold-rolled, decarburized and steep annealed, aluminum is subjected to hot-dip galvanizing, and then aluminum subjected to final annealing is plated Directional electrical steel.
Further, it may be a directional electric steel sheet plated with aluminum-silicon plated with aluminum-silicon after decarburization and steep annealing.
Also, it may be a directional electrical steel sheet having a N content of 20 to 50 ppm after the slab is heated.
Further, the method may further include the step of annealing the hot-rolled sheet after the hot-rolling, and the average size of the precipitates in the steel sheet after annealing the hot-rolled sheet may be 200 to 3000 ANGSTROM.
The grain-oriented electrical steel sheet according to the present invention controls Al in the steelmaking step within an appropriate range to suppress the formation of coarse nitride in the decarburization annealing and steep annealing steps. In the subsequent step, Al is diffused into the steel sheet to increase the resistivity, and it is possible to provide a grain-oriented electrical steel sheet having low iron loss and excellent magnetic properties.
Advantages and features of the present invention and methods of achieving them will become apparent with reference to the embodiments described in detail below.
However, it is to be understood that the present invention is not limited to the disclosed embodiments, but may be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. It is intended that the disclosure of the present invention be limited only by the terms of the appended claims.
The grain-oriented electrical steel sheet according to an embodiment of the present invention may contain 2.0 to 6.5% of Si, 0.20% or less of Mn (not including 0%), 0.01% or less of N (not including 0% , S: not more than 0.01% (excluding 0%), P: 0.005 to 0.05%, C: 0.04 to 0.12%, B: 0.001 to 0.05 wt%, and the balance includes Fe and other inevitably incorporated impurities , And aluminum is a hot-dip galvanized steel sheet.
The electrical steel sheet may be a directional electrical steel sheet in which aluminum-silicon is hot-dip coated.
The method of manufacturing a grain-oriented electrical steel sheet according to an embodiment of the present invention includes: 2.0 to 6.5% of Si, 0.040% or less of Al (not including 0%), 0.20% or less of Mn (including 0% 0.01% or less (not including 0%), S: 0.01% or less (excluding 0%), P: 0.005 to 0.05%, C: 0.04 to 0.12% Providing a slab comprising Fe and other inevitably incorporated impurities; Reheating the slab; Hot-rolling the slab to produce a hot-rolled steel sheet; Cold-rolling the hot-rolled steel sheet to produce a cold-rolled steel sheet; Subjecting the cold-rolled steel sheet to decarburization annealing and steep annealing; And a step of hot-dipping aluminum molten metal on the electric steel sheet after the decarburization annealing and the steep annealing have been completed; And applying an annealing separator to perform final annealing; .
The step of hot-dip coating may be a step of hot-dipping the aluminum-silicon molten metal.
The reason for limiting the components of the present invention will be described.
[Si: 2.0 to 6.5 wt%]
Si is a basic composition of an electric steel sheet and plays a role of lowering the core loss by increasing the resistivity of the material.
When the Si content is less than 2.0 wt%, the resistivity is decreased, and the eddy current loss is increased to deteriorate the iron loss characteristic. In addition, during high temperature annealing, phase transformation between ferrite and austenite occurs, and the secondary recrystallization becomes unstable as well as the structure is severely damaged.
When the Si content exceeds 6.5 wt%, the magnetostrictive property and the magnetic permeability are remarkably poor.
[Al: 0.04 wt% or less]
In addition to AlN precipitated at the time of hot rolling and annealing of hot-rolled steel sheet, Al also has nitrogen ions introduced by ammonia gas in the annealing step after cold rolling combined with Al, Si and Mn existing in solid state in steel, Si, < / RTI > Mn) N and AlN type nitride to form a strong grain growth inhibitor.
However, when the Al content exceeds 0.040 wt% in the slab, a coarse nitride is formed and the grain growth inhibiting ability is deteriorated, and the steel loss and the magnetism are adversely affected.
[Mn: 0.20 wt% or less]
Mn has an effect of reducing the total iron loss by decreasing the eddy current loss by increasing the resistivity and reacting with the nitrogen introduced by the nitriding treatment together with Si to form precipitates of N (Al, Si, Mn) Which causes secondary recrystallization.
When Mn is more than 0.20 wt%, a large amount of (Fe, Mn) and Mn oxide are formed on the surface of the steel sheet in addition to Fe 2 SiO 4 , thereby hindering formation of a base coat formed during high temperature annealing, Since the phase transformation between ferrite and austenite is induced, the aggregate structure is seriously damaged and magnetic properties are greatly deteriorated. Therefore, the content of Mn is 0.20 wt% or less.
[N: 0.01 wt% or less]
N is preferably added in an amount of 0.01 wt% or less as an element that reacts with Al to form AlN.
If N is more than 0.01 wt%, surface defects due to nitrogen diffusion are caused in the step after hot rolling, excessive nitrides are formed in the slab state and the rolling property is lowered, thereby complicating the subsequent steps and increasing the manufacturing cost do.
Further, in the annealing step after the cold rolling, N necessary for further forming nitrides such as N and AlN during the nitriding treatment using ammonia gas (Al, Si, Mn) can be reused.
[C: 0.04 to 0.12 wt%]
C is an element that causes phase transformation between ferrite and austenite and is an essential element for improving the rolling property of an electric steel sheet having a high brittleness and poor rolling property, but a carbide formed due to a magnetic aging effect when remaining in the final product It is an element that deteriorates magnetic properties.
If the content of C is less than 0.04 wt% in the range of the Si content according to the present invention, the phase transformation between the ferrite and the austenite does not occur, resulting in nonuniformity of slab and hot rolled microstructure.
If it exceeds 0.12 wt%, not only a sufficient decarburization effect can not be obtained in the decarburization annealing process but also the secondary recrystallization texture is damaged due to the phase transformation phenomenon and the magnetic properties are deteriorated due to magnetic aging .
[S: 0.010 wt% or less]
S is an important element that reacts with Mn to form MnS.
When S is contained in an amount of 0.01 wt% or more, precipitates of MnS are formed in the slab to inhibit grain growth and it is difficult to control the microstructure in the subsequent process due to segregation at the center of the slab during casting.
Further, since MnS is not used as a grain growth inhibitor in the present invention, S is preferably not added. However, it is preferably 0.01 wt% or less in consideration of the amount that is inevitably incorporated in the steelmaking process.
[P: 0.005 to 0.05 wt%]
P segregates in grain boundaries and interferes with grain boundary movement and at the same time plays an auxiliary role of suppressing grain growth.
In addition, there is an effect of improving {110} < 001 >
When the content of P is less than 0.005 wt%, the effect of addition is not exhibited. When the content of P is more than 0.05 wt%, the brittleness is increased and the rolling property is greatly deteriorated.
A process for producing a grain-oriented electrical steel sheet using slabs having the above composition will be described.
The slab having the above composition is reheated. In the step of reheating the slab, the total amount of nitrogen reused in the slab may be 20 to 50 ppm.
The amount of reused N should be considered in consideration of the content of Al contained in the liquefied natural gas, because the nitrides used as the grain growth inhibitors are (Al, Si, Mn) N and AlN.
That is, the reused N is influenced by the size and amount of the additional AlN formed in the decarburized annealing step. If the size of the AlN is the same, if the amount is larger, the grain growth restraining force is increased and a suitable secondary recrystallization The microstructure can not be obtained.
On the contrary, if the amount is too small, the crystal growth driving force of the primary recrystallized microstructure is increased, so that an appropriate secondary recrystallized microstructure can not be obtained similarly to the above-mentioned phenomenon.
In addition, it is preferable that the slab is reheated in a temperature range in which N and S which are dissolved in the step of reheating the slab are incompletely dissolved.
If N and S are completely dissolved, a large amount of nitride or sulfide is formed after annealing of the hot-rolled steel sheet, which makes it impossible to perform hot rolling once, which is a subsequent process, .
In addition, since the size of the primary recrystallized grains becomes considerably fine, proper secondary recrystallization can not be developed. For incomplete solution casting, it is preferable to reheat the slab to a temperature of 1250 DEG C or less.
The reheated slab is hot-rolled to produce a hot-rolled steel sheet.
Further, the hot-rolled steel sheet may further include a step of annealing the hot-rolled steel sheet.
In the hot-rolled hot-rolled sheet, there is a deformed structure stretched in the rolling direction due to the stress, and AlN or MnS precipitates during hot rolling.
Therefore, annealing of the hot-rolled sheet is carried out to obtain uniform recrystallized microstructure and fine AlN precipitate distribution before cold rolling.
The annealing temperature of the hot-rolled sheet is preferably heated to 900 to 1200 ° C in order to maximize the austenite fraction, and then subjected to a crack heat treatment and then cooled.
The average size of the precipitate in the strip after annealing the hot-rolled sheet after applying the heat treatment described above may range from 200 to 3000 Å.
After the hot-rolled sheet annealing, cold-rolling is performed in a thickness of 0.10 mm to 0.50 mm, and a one-time cold rolling is performed without rolling annealing of the deformed structure in the middle, desirable.
With one strong cold rolling, orientations with low degrees of integration in the {110} < 001 > orientation are rotated in the direction of the deformation, and only the gothese grains best aligned with the {110} < 001 > orientation are present in the cold rolled plate.
Therefore, in the two or more rolling methods, orientations having a low degree of integration are also present in the cold-rolled steel sheet, and secondary recrystallization is similarly performed at the time of the final high-temperature annealing to obtain low magnetic flux density and iron loss.
Therefore, it is preferable that the cold rolling is performed at a cold rolling rate of 87% or more by one time of cold rolling.
The cold-rolled cold-rolled steel sheet is subjected to decarburization and immersion treatment using ammonia gas.
In order to deposit N, AlN, (B, Si, Mn) N, (Al, B) N and BN which are the crystal grain growth inhibitors (Al, Si, Mn) using ammonia gas, after decarburization and recrystallization, It can be nitrided by using gas.
Or a method of simultaneously injecting ammonia gas so that decarburization and nitriding treatment can be performed at the same time, but the present invention is not limited thereto.
In the decarburization treatment and the nitriding treatment, the annealing temperature of the steel sheet is preferably in the range of 800 to 950 ° C.
If the annealing temperature of the steel sheet is as low as 800 ° C or less, it takes a long time to decarburize and the SiO 2 oxide layer is densely formed on the surface of the steel sheet to cause base coating defects. When heated to 950 ° C or more, And the crystal growth driving force is lowered so that stable secondary recrystallization is not formed.
Annealing time can be processed within 5 minutes considering productivity.
Some or all of the oxide layers existing in the external oxide layer formed on the surface of the steel sheet in a reducing atmosphere immediately before the completion of the decarburization annealing and the nitriding annealing or after the completion of the decarburization annealing and the annealing of the nitrided steel are reduced and removed, The silicon-containing metal is subjected to hot-dip coating.
When the aluminum or aluminum-silicon melting metal is subjected to hot-dip coating, the temperature is preferably 600 to 900 占 폚.
If the molten metal is inhomogeneously melted when the temperature is lower than 600 ° C., the quality of the molten metal is lowered, and when the molten metal is melted at a temperature exceeding 900 ° C., the surface wettability of the molten metal and the nitrided nitrile Thereby deteriorating the quality of the hot dip coating.
The steel sheet after completion of the hot-dip coating of aluminum or aluminum-silicon is subjected to final annealing after application of the annealing separator to cause secondary recrystallization so that the {110} face of the steel sheet is parallel to the rolled surface, and the <001> direction is parallel to the rolling direction A {110} < 001 > aggregate structure is formed to produce a directional electrical steel sheet having excellent magnetic properties.
{110} < 001 > aggregate structure formed by secondary recrystallization is formed at the final annealing, and impurities which impair magnetic properties are removed.
Also, since the molten plated aluminum diffuses and penetrates into the steel sheet, the aluminum content of the steel sheet is increased, and the resistivity is increased, so that the magnetic properties of the oriented electrical steel sheet are excellent.
As the final annealing method, the nitride is inhibited by keeping the mixed gas of nitrogen and hydrogen at the temperature rising period before the secondary recrystallization, so that the secondary recrystallization is well developed. After completion of the secondary recrystallization, Keep it for a long time to remove impurities.
Hereinafter, the present invention will be described more specifically by way of examples.
[Example 1]
The balance of Fe, and other inevitable components, the balance being Fe and other inevitable elements, The slabs containing the impurities contained therein were reheated to a temperature of 1200 캜.
Thereafter, hot-rolled at 2.3 mm. The hot rolled sheet was heated to a temperature of 1050 占 폚, maintained at 950 占 폚 for 180 seconds, and quenched in water.
The steel sheet was pickled, and then subjected to one-time cold-rolling at a thickness of 0.23 mm. The cold-rolled sheet was held at a temperature of 870 ° C for 180 seconds in a humid atmosphere of hydrogen and a mixed gas of nitrogen and ammonia, Followed by nitriding annealing.
The steel sheet was subjected to final annealing after dissolving aluminum or aluminum-25% silicon binary binary molten metal as shown in Table 1.
In the final annealing, a mixed atmosphere of 25% nitrogen and 75% hydrogen was set up to 1200 ° C., and after reaching 1200 ° C., it was maintained in a 100% hydrogen atmosphere for 10 hours or more.
Table 1 shows the measured values of magnetic properties for each condition.
As can be seen from the above Table 1, it can be seen that the inventive ash material obtained by hot-dipping aluminum or an aluminum-silicon alloy has remarkably improved iron loss characteristics while having the same magnetic flux density as the comparative material.
While the present invention has been described in connection with certain exemplary embodiments, it will be understood by those skilled in the art that various changes and modifications may be made without departing from the spirit and scope of the invention as defined by the appended claims.
It is therefore to be understood that the above-described embodiments are illustrative in all aspects and not restrictive. The scope of the present invention is defined by the appended claims rather than the detailed description, and all changes or modifications derived from the meaning and scope of the claims and their equivalents should be interpreted as being included in the scope of the present invention .
Claims (16)
Reheating the slab;
Hot-rolling the slab to produce a hot-rolled steel sheet;
Cold-rolling the hot-rolled steel sheet to produce a cold-rolled steel sheet;
Subjecting the cold-rolled steel sheet to decarburization annealing and steep annealing; And
Plating aluminum on the electric steel sheet after the decarburization annealing and the steep annealing have been completed;
Applying an annealing separator to perform final annealing;
Wherein the method comprises the steps of:
Wherein the plating step comprises plating aluminum-silicon.
Wherein the plating temperature in the plating step is 600 to 900 占 폚.
Wherein the total amount of nitrogen recycled to the slab is 20 to 50 ppm in the step of reheating the slab.
Wherein the reheating temperature in the step of reheating the slab is a temperature range in which N and S to be dissolved are incompletely dissolved.
Wherein the temperature range for incompletely fusing is 1250 DEG C or less.
Further comprising the step of annealing the hot rolled steel sheet by hot rolling,
Wherein the average size of the precipitates in the steel sheet after annealing the hot-rolled sheet is 200 to 3000 angstroms.
Wherein the step of producing the cold-rolled steel sheet comprises a step of rolling the steel sheet at a ratio of not less than 87%
Wherein the decarburization annealing and the steep annealing are performed at 800 to 950 占 폚.
Wherein the final annealing is performed in a mixed atmosphere of nitrogen and hydrogen gas in a temperature rising period before the secondary recrystallization and in a hydrogen atmosphere after completion of secondary recrystallization.
Wherein the step of performing the decarburization annealing and the steep annealing of the cold-rolled steel sheet is performed simultaneously with the decarburization annealing and the steep annealing.
Wherein the electrical steel sheet is plated with aluminum-silicon.
Wherein the heated slab is subjected to hot rolling and then hot rolled sheet annealing, and the average size of the precipitates in the steel sheet after annealing the hot rolled steel sheet is 200 to 3000 Å.
Wherein the electrical steel sheet is plated with aluminum-silicon.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020130161899A KR20150073799A (en) | 2013-12-23 | 2013-12-23 | Oriented electrical steel sheet and method for manufacturing the same |
| CN201410806719.4A CN104726662B (en) | 2013-12-23 | 2014-12-22 | Oriented electrical steel and its manufacture method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020130161899A KR20150073799A (en) | 2013-12-23 | 2013-12-23 | Oriented electrical steel sheet and method for manufacturing the same |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| KR1020160006143A Division KR101621053B1 (en) | 2016-01-18 | 2016-01-18 | Oriented electrical steel sheet and method for manufacturing the same |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| KR20150073799A true KR20150073799A (en) | 2015-07-01 |
Family
ID=53787245
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| KR1020130161899A KR20150073799A (en) | 2013-12-23 | 2013-12-23 | Oriented electrical steel sheet and method for manufacturing the same |
Country Status (1)
| Country | Link |
|---|---|
| KR (1) | KR20150073799A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2020149334A1 (en) * | 2019-01-16 | 2020-07-23 | 日本製鉄株式会社 | Grain-oriented electrical steel sheet, intermediate steel sheet for grain-oriented electrical steel sheet, and manufacturing method thereof |
| CN115066512A (en) * | 2019-12-18 | 2022-09-16 | Posco公司 | Non-oriented electrical steel sheet and method for manufacturing the same |
-
2013
- 2013-12-23 KR KR1020130161899A patent/KR20150073799A/en active Application Filing
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2020149334A1 (en) * | 2019-01-16 | 2020-07-23 | 日本製鉄株式会社 | Grain-oriented electrical steel sheet, intermediate steel sheet for grain-oriented electrical steel sheet, and manufacturing method thereof |
| JPWO2020149334A1 (en) * | 2019-01-16 | 2021-11-25 | 日本製鉄株式会社 | Grain-oriented electrical steel sheets, intermediate steel sheets for grain-oriented electrical steel sheets, and their manufacturing methods |
| CN115066512A (en) * | 2019-12-18 | 2022-09-16 | Posco公司 | Non-oriented electrical steel sheet and method for manufacturing the same |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR101693522B1 (en) | Grain oriented electrical steel having excellent magnetic properties and method for manufacturing the same | |
| KR101676630B1 (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR100797997B1 (en) | Method for manufacturing grain-oriented electrical steel sheets with excellent magnetic property and high productivity | |
| JP7221481B2 (en) | Grain-oriented electrical steel sheet and manufacturing method thereof | |
| KR101633629B1 (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR101506677B1 (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR20150073799A (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR101540375B1 (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| CN113195770B (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR101667617B1 (en) | Grain-oriented electrical steel sheet and method for manufacturing the same | |
| US11530462B2 (en) | Grain-oriented electrical steel sheet and manufacturing method therefor | |
| KR101621053B1 (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR101263842B1 (en) | Grain-oriented electrical steel sheets with extremely low core-loss and high flux-density and Method for manufacturing the same | |
| KR101621056B1 (en) | Method for manufacturing oriented electrical steel sheet | |
| KR101263841B1 (en) | Method for manufacturing grain-oriented electrical steel sheets with extremely low core-loss and high flux-density | |
| KR101408231B1 (en) | Method for manufacturing the grain-oriented electrical steel sheets with excellent magnetic properties | |
| KR101568835B1 (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR101510271B1 (en) | Method for manufacturing the grain-oriented electrical steel sheets with excellent magnetic properties | |
| KR101263796B1 (en) | Grain-oriented electrical steel sheets with extremely low core-loss and high flux-density and Method for manufacturing the same | |
| KR20150073795A (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR101535933B1 (en) | Oriented electrical steel sheet and method for manufacturing the same | |
| KR101459730B1 (en) | Oriented electrical steel sheets and method for manufacturing the same | |
| KR101263798B1 (en) | Grain-oriented electrical steel sheets with extremely low core-loss and high flux-density and Method for manufacturing the same | |
| KR20190077965A (en) | Manufacturing method of oriented electrical steel sheet |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A201 | Request for examination | ||
| E902 | Notification of reason for refusal | ||
| AMND | Amendment | ||
| E601 | Decision to refuse application | ||
| AMND | Amendment | ||
| A107 | Divisional application of patent |