CN116770176A - Non-oriented electrical steel for new energy automobile driving motor and manufacturing method thereof - Google Patents
Non-oriented electrical steel for new energy automobile driving motor and manufacturing method thereof Download PDFInfo
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- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 title claims abstract description 30
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 238000000137 annealing Methods 0.000 claims abstract description 39
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 38
- 238000000034 method Methods 0.000 claims abstract description 18
- 229910052742 iron Inorganic materials 0.000 claims abstract description 16
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- 238000005097 cold rolling Methods 0.000 claims description 26
- 238000010438 heat treatment Methods 0.000 claims description 15
- 238000005098 hot rolling Methods 0.000 claims description 14
- 229910052739 hydrogen Inorganic materials 0.000 claims description 12
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 9
- 239000001257 hydrogen Substances 0.000 claims description 9
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
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- 229910000976 Electrical steel Inorganic materials 0.000 abstract description 10
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Abstract
The application provides non-oriented electrical steel for a new energy automobile driving motor and a manufacturing method thereof, wherein the non-oriented electrical steel comprises the following components: c:0.001-0.005%, si:3.2-3.5%, mn:0.35-0.65%, al:0.50-0.80%, P: less than or equal to 0.02 percent, S: less than or equal to 0.005%, less than or equal to 0.010% and less than or equal to 0.020% of Ce+Sn, and the balance of iron and unavoidable impurities. Compared with the prior art, the application purifies the steel and microalloys to improve the strength and magnetic property of the non-oriented silicon steel, can inhibit the annoyance of an inner oxide layer to generate reduced hysteresis loss, can increase favorable texture proportion, smaller grains and favorable texture for the process sectional control of annealing temperature, optimizes the uniformity of the grain size, and ensures that the produced non-oriented electrical steel has higher yield strength and good magnetic induction while obtaining favorable medium-high frequency iron loss.
Description
Technical Field
The application belongs to the technical field of metallurgical materials, in particular to non-oriented electrical steel for a new energy automobile driving motor and a manufacturing method thereof.
Background
Along with the improvement of environmental protection requirements, new energy automobiles are used as environmental protection type riding instead of walking tools, and the development is faster and faster; the driving motor is one of the core components of the new energy automobile, and needs to meet the requirements of miniaturization, high efficiency and high torque. The miniaturization and high efficiency of the motor require that the non-oriented electrical steel for manufacturing the iron core has low iron loss and high magnetic induction; with the increase of the rotation speed, the motor rotor is easily damaged by huge centrifugal force, so that the non-oriented electrical steel is required to have higher strength to ensure the safety at high rotation speed.
The traditional non-oriented silicon steel can meet the requirements of low iron loss and high magnetic induction, but has lower strength, strength and iron loss are contradictory indexes, and the improvement of strength can reduce the magnetic performance, so that the development of the non-oriented electrical steel for the low-iron loss and high-strength new energy automobile driving motor is an important research task.
Disclosed in patent publication No. CN102747291A published in 10/24/2012, a non-oriented silicon steel strip with excellent high-frequency low-iron-loss magnetism and a production method thereof comprise the following components in percentage by weight: 0.001-0.005 of C, 2.05-3.75 of Si, 0.150-0.850 of Als, less than or equal to 0.003 of N, less than or equal to 0.005 of S, less than or equal to 0.02 of P, 0.15-0.30 of Mn, 0.01-0.08 of Sn, 2.5-3.5 of Cr, 0.05-0.1 of Cu, less than or equal to 0.003 of Ti, and the balance of Fe and unavoidable impurities; the low-iron-loss and high-strength silicon steel thin strip is obtained by adding elements such as Sn, cr, cu and the like and adopting a high-temperature hot rolling and secondary cold rolling method, but the improvement degree of magnetic induction is limited, and the magnetic induction of the non-oriented silicon steel is lower. And elements such as Cu are added to improve the strength, but Cu is added to cause copper embrittlement, so that the rolling difficulty is increased, high-temperature annealing is needed to temporarily dissolve Cu, recrystallization is delayed, and the grains are abnormally grown at a higher heating temperature, so that the strength is not improved.
The patent with publication number CN103667900A published in 3 month 26 of 2014 discloses a preparation method of high magnetic induction silicon steel for an automobile motor, elements such as Sn, bi, ce, er are added, and extremely complex production methods such as hot rolling and secondary cold rolling are adopted, so that a high magnetic induction silicon steel product is finally obtained, but the production method of the method is complex, the requirement on equipment transformation is high, the industrial production efficiency is seriously reduced, and the alloy cost of the product is obviously increased by the elements such as Sn, bi, ce, er added in the patent, so that the method is not suitable for industrial production.
Disclosure of Invention
The application aims to provide non-oriented electrical steel for a new energy automobile driving motor and a manufacturing method thereof, and the non-oriented electrical steel is prepared by reasonably proportioning rare earth and Sn and combining smelting, hot rolling, normalizing, cold rolling and annealing process design, so that the high-strength non-oriented silicon steel with excellent magnetic performance is finally obtained, and has lower iron loss and higher strength.
The specific technical scheme of the application is as follows:
the non-oriented electrical steel for the new energy automobile driving motor comprises the following components in percentage by mass:
c:0.001-0.005%, si:3.2-3.5%, mn:0.35-0.65%, al:0.50-0.80%, P: less than or equal to 0.02 percent, S: less than or equal to 0.005%, less than or equal to 0.010% and less than or equal to 0.020% of Ce+Sn, and the balance of iron and unavoidable impurities.
The components of the non-oriented electrical steel for the new energy automobile driving motor also meet the following conditions: C+S+N+Ti is less than or equal to 0.0048%, nb+V+Ti+Zr is less than or equal to 0.0030%, and the residual element is controlled;
the components of the non-oriented electrical steel for the new energy automobile driving motor also meet the following conditions: ce/sn=0.25-2.0.
The thickness of the non-oriented electrical steel for the new energy automobile driving motor is 0.25mm;
the grain size of the structure of the non-oriented electrical steel for the new energy automobile driving motor is 70-120 mu m;
the non-oriented electrical steel for the new energy automobile driving motor has the product performance of B 50 ＝1.69-1.72T，W 1.0/400 11.0-12.2W/Kg, yield strength R el 450-470MPa, tensile strength R m 550-600MPa, elongation A 50 18-20％。
The application provides a manufacturing method of non-oriented electrical steel for a new energy automobile driving motor, which comprises the following steps: smelting, heating a plate blank, hot rolling, coiling, normalizing, pickling, first cold rolling, intermediate annealing, second cold rolling and annealing;
the smelting controls the impurity elements of steelmaking components to be C+S+N+Ti less than or equal to 0.0048 percent, and Nb+V+Ti+Zr less than or equal to 0.0030 percent;
the hot rolling and coiling are carried out, the thickness of a hot plate is controlled to be 1.8mm-2.4mm, the hot rolling and coiling are carried out, then the heat preservation is carried out at 500-700 ℃ for 0.1-10 h, and the heat preservation is carried out and then the hot plate is slowly cooled in protective gas; the protective gas is N with the volume ratio of 50-100% 2 And 0-50% H 2 。
Trimming the steel plate before normalizing pickling, wherein the width of each side of the trimming is 0.5-5 mm;
the normalizing acid washing is carried out, the normalizing temperature is 850-950 ℃, and the temperature is kept for 30-500 s;
the first cold rolling is carried out, and the rolling reduction is controlled to be 50% -85%;
the intermediate annealing is carried out at the annealing temperature of 800-950 ℃;
the intermediate annealing specifically comprises the following steps: heating the slab subjected to the first cold rolling to a target temperature of 800-950 ℃ at a heating rate of more than or equal to 100 ℃/s, and then preserving heat for 20-60 s; the application adopts high Si content of 3.2-3.5%, the phase transition point temperature is 800-870 ℃, the temperature is raised from room temperature to 800-950 ℃, the temperature raising rate is kept at 200 ℃/s, the hydrogen volume content in the atmosphere in the annealing furnace is controlled to be more than or equal to 30%, the balance is nitrogen, and the grain size of the steel plate is controlled to be 70-90 mu m after the section is heated and annealed.
The second cold rolling is carried out, and the thickness is rolled to a target thickness; the second cold rolling adopts three times of rolling, the first pass reduction rate is more than 35 percent, so that better grain breakage is obtained, more fibrous tissues are obtained later, and more nucleation points are provided for subsequent annealing growth.
The annealing is performed after the second cold rolling, and the annealing is performed in three sections;
the first section: raising the temperature from room temperature to 400-600 ℃, wherein the condition that crystal grains grow up can not occur in the temperature range below the phase transition temperature, and a temperature foundation is mainly provided for the follow-up; the hydrogen volume content of the annealing furnace atmosphere is more than or equal to 30%, and the balance is nitrogen, so that the hysteresis loss and the iron loss are prevented from being influenced by surface oxidation in the region and the grain boundary oxidation of the subsequent rapid temperature rising region of oxygen atoms adsorbed on the surface of the steel plate.
And a second section: the temperature is raised from 400-600 ℃ to above the phase transition temperature, the heat conductivity coefficient is reduced along with the increase of the silicon content by taking the difference between the annealing furnace temperature and the plate surface temperature of 30-60 ℃ into consideration, the temperature is set to be 400-600 ℃ to 910-950 ℃ through the heat conductivity coefficient test of 20-30W/(m.K), the temperature is quickly raised, the electric heating temperature raising mode is adopted, the temperature raising rate is controlled to be more than 200 ℃/s, the high-reducibility atmosphere is maintained, the hydrogen volume content is controlled to be more than or equal to 35%, and the balance is nitrogen. This interval is mainly to increase the {100} and {110} component ratios and decrease the {111} component ratio. The second stage is heated from 400-600 deg.c to 910-950 deg.c, mainly in the grain growing interval, to provide great driving force in the effective area and raise the heating rate, and the second stage annealing process is set in consideration of Sn and Si content.
Third section: the temperature is raised from 910-950 ℃ to 980-1050 ℃, the temperature raising rate is controlled below 100 ℃/s, the heat preservation time is 5s-30s, and the hydrogen volume content is kept to be more than or equal to 30%. Decreasing the rate of temperature rise at this stage mainly prevents the {111} component from increasing, and the high temperature is mainly to increase the uniformity of grain size.
And after the third section of heat preservation, cooling at a cooling rate of less than or equal to 10 ℃/s.
In the annealing process, the dew point in the annealing furnace is controlled to (-40) DEG C- (-10) DEG C, and the tension in the furnace is controlled to 0.1Mpa-9Mpa.
After annealing, an insulating material coating is performed.
In the application, C: the present application controls the C content, and the C in solid solution form or cementite form can damage the magnetic properties of the steel sheet, and the present application limits the C content to less than 0.005%.
Si: the Si content is improved, the strength of the steel plate is improved, the magnetic induction is reduced, the resistivity is increased, the hysteresis loss is reduced, the difficulty in controlling the surface quality of the hot rolled coil is increased, and the Si content is 3.20-3.50%.
Mn: mn is beneficial to improving the resistivity of the electrical steel and reducing the iron loss. But also by improving the rollability of the hot rolled sheet. Therefore, the Mn content is increased by the present application to be set to 0.35-0.65%.
Al: the Al content is improved, the strength of the steel plate is improved, and the magnetic induction is improved, but the excessive Al content is easy to cause the adhesion of molten steel, so the Al content is controlled to be 0.50-0.80%.
P: p is promoted by Sn to generate segregation, fine grains, strength and texture, but Fe 3 P segregation can embrittle the steel plate and reduce toughness, so that the P content is controlled to be less than or equal to 0.020%.
S: s and Mn in steel can form plastic MnS inclusion to reduce thermal embrittlement, but strip steel can form strip structure to reduce toughness and formability of steel plate, and S has great influence on magnetic performance, and the S content is controlled to be less than or equal to 0.005%.
Ce+sn: ce is easy to form oxysulfide of Ce with impurity elements such as O, S in steel in the steelmaking process, the effect of purifying the steel is achieved, the magnetic performance is improved, the Sn element is segregated and an oxide layer on the surface of the steel plate is optimized, and the texture component is optimized so as to further improve the magnetic induction; sn can be offset at the original grain boundary in the hot rolling process, and promote P offset, prevent crystal grains from growing, refine the crystal grains and improve the strength of the steel plate. However, the grain refinement can cause the increase of hysteresis loss, and because Sn and P are offset to improve the texture, the influence of offset on the magnetic induction is reduced, and the content of Ce+Sn is controlled to be 0.010-0.020%. In addition, since the grain size is reduced due to Sn element segregation, hysteresis loss is increased due to smaller grain return, and therefore, the grain size is coarsened by adding Ce and increasing nucleation speed; the Ce element coarsens the grain size mainly through coarsening sulfide, but the larger grain size has a reducing effect on magnetic induction and reduces mechanical properties, so that the Ce/Sn=0.25-2.0 is set for balancing a plurality of indexes.
The inventor utilizes the characteristics of Sn element microalloying and Ce oxysulfide for purifying steel and refining grains, and reasonable component proportion and process, improves the strength and the uniformity of the grains, reduces the iron loss, promotes the formation of favorable textures and improves the magnetic performance. Meanwhile, the distribution of the rolling reduction of the secondary cold rolling method and the optimization of the intermediate annealing process are utilized to be beneficial to the uniform distribution of textures and grains; the adopted three-stage annealing increases the uniformity of grain size and increases the beneficial components; while reducing the cooling rate reduces the generation of internal stresses.
Compared with the prior art, the application purifies the steel and microalloys to improve the strength and magnetic property of the non-oriented silicon steel, can inhibit the formation of an inner oxide layer to reduce hysteresis loss, increases favorable texture proportion, smaller grains and favorable texture for annealing temperature process sectional control, optimizes the uniformity of the grain size, and obtains the grain size of 70-120 mu m, so that the produced non-oriented electrical steel has higher yield strength and favorable magnetic induction while obtaining favorable medium-high frequency iron loss.
Drawings
FIG. 1 is a diagram of example 1 with grain size 90 μm, improved advantageous texture and composition, reduced hysteresis loss, and more uniform grain size;
fig. 2 is a graph of comparative example 1 with larger grain size and non-uniformity.
Detailed Description
The present application will be described with reference to examples.
Example 1-example 2
The non-oriented electrical steel for the new energy automobile driving motor comprises the following components in percentage by mass: as shown in scheme 1 of Table 1, and C+S+N+Ti is less than or equal to 0.0048%, nb+V+Ti+Zr is less than or equal to 0.0030%; the balance not shown in table 1 is Fe and unavoidable impurities.
TABLE 1 Steel Components (wt%) of examples 1 and 2 respectively
| Scheme for the production of a semiconductor device | C | Si | Sn | Mn | P | S | Al | N | Ce |
| Scheme 1 | 0.0006 | 3.48 | 0.012 | 0.49 | ≤0.01 | 0.0002 | 0.65 | 0.0003 | 0.005 |
| Scheme 2 | 0.0006 | 3.48 | 0 | 0.49 | ≤0.01 | 0.0002 | 0.65 | 0.0003 | 0.005 |
| Scheme 3 | 0.0006 | 3.48 | 0.012 | 0.49 | ≤0.01 | 0.0002 | 0.65 | 0.0003 | 0 |
Comparative example 1-comparative example 3
The non-oriented electrical steel for the new energy automobile driving motor comprises the following components in percentage by mass: as shown in scheme 1 of Table 1, and C+S+N+Ti is less than or equal to 0.0048%, nb+V+Ti+Zr is less than or equal to 0.0030%; the balance not shown in table 1 is Fe and unavoidable impurities.
Comparative example 4
The non-oriented electrical steel for the new energy automobile driving motor comprises the following components in percentage by mass: as shown in scheme 2 of Table 1, and C+S+N+Ti is less than or equal to 0.0048%, nb+V+Ti+Zr is less than or equal to 0.0030%; the balance not shown in table 1 is Fe and unavoidable impurities.
Comparative example 5
The non-oriented electrical steel for the new energy automobile driving motor comprises the following components in percentage by mass: as shown in scheme 3 of Table 1, and C+S+N+Ti is less than or equal to 0.0048%, nb+V+Ti+Zr is less than or equal to 0.0030%; the balance not shown in table 1 is Fe and unavoidable impurities.
The manufacturing method of the non-oriented electrical steel for the new energy automobile driving motor of each of the above examples and comparative examples includes the following steps: smelting, preparing a plate blank, heating the plate blank, hot rolling and coiling, normalizing and pickling, first cold rolling, intermediate annealing, second cold rolling, annealing and insulating material coating;
the method comprises the following steps:
the impurity elements of steelmaking components are controlled to be less than or equal to 0.0048 percent of C+S+N+Ti, and less than or equal to 0.0030 percent of Nb+V+Ti+Zr; hot rolling to control the thickness of the hot plate to be 2.0mm, coiling, then heat-preserving at 650 ℃ for 0.5h, and preserving heat at a volume fraction of 60N 2 +40% H 2 Slowly cooling;
then carrying out trimming treatment on the steel plate, wherein the width of each side of the trimming is 0.5mm-5mm;
carrying out normalized acid washing, wherein the conventional temperature is 870 ℃, and the temperature is kept for 120 seconds;
performing first cold rolling, controlling the rolling reduction to 70%, and performing cold rolling to a thickness of 0.60 mm;
and then carrying out intermediate annealing: heating the slab subjected to the first cold rolling to the target temperature of 900 ℃ at the heating rate of 200 ℃/s, and then preserving heat for 40s; the hydrogen volume content of the atmosphere in the annealing furnace is controlled to be more than or equal to 30 percent, the balance is nitrogen, and the grains are controlled to be 70-90 mu m after the annealing furnace is heated in the section.
The second cold rolling adopts three times of rolling, and the first rolling reduction rate is 38%; cold rolling to 0.25mm after three times of cold rolling;
finally, annealing is carried out, and the process is divided into three sections;
the first section: raising the temperature from room temperature to 400-600 ℃ at a heating rate of 20 ℃/s; the hydrogen volume content of the annealing furnace atmosphere is more than or equal to 30%, and the balance is nitrogen, so that the influence of hysteresis loss and iron loss caused by surface oxidation in the interval and the influence of grain boundary oxidation of oxygen atoms adsorbed on the surface of the steel plate in a subsequent rapid heating area can be prevented.
And a second section: the temperature is increased from 400-600 ℃ to above the phase transition temperature, the heat conductivity coefficient is reduced along with the increase of the silicon content by taking the general difference between the furnace temperature and the plate surface temperature of 30-60 ℃ into consideration, the temperature is set to 400-600 ℃ to 910-950 ℃ through the heat conductivity coefficient test of 20-30W/(m x K), the temperature is rapidly increased, the heating rate is controlled to be above 200 ℃/s by adopting an electric heating mode, the high-reducibility atmosphere is maintained, the hydrogen content is controlled to be more than or equal to 38% by volume, and the balance is nitrogen. This interval is mainly to increase the {100} and {110} component ratios and decrease the {111} component ratio.
Third section: the temperature is controlled between 910 ℃ to 950 ℃ and 980 ℃ to 1050 ℃, the temperature rising rate is controlled at 20 ℃/s, the heat preservation time is 25s, the hydrogen volume content is kept to be more than or equal to 38%, and the balance is nitrogen; after the heat preservation, cooling was performed at a cooling rate of 8 ℃/s.
The dew point in the annealing furnace is controlled at (-40) deg.C- (-10) deg.C, and the tension in the furnace is controlled at 0.1Mpa-9Mpa.
The annealed steel coil is coated with a semi-organic coating (insulating material coating) to ensure insulativity and interlayer resistance.
Specific process parameters of the annealing sections of each example and comparative example are shown in Table 2, the thickness of the produced steel is 0.25mm, and the performance test is shown in Table 2.
Table 2 steel production process and properties of each of examples and comparative examples
The underlined data above are not satisfactory for the present application.
As can be seen from the examples and comparative examples, the product grain size is small and uniform and the product properties are produced according to the composition and production parameter control of the present applicationSatisfy B 50 ＝1.69-1.72T，W 1.0/400 ＝
11.0-12.2W/Kg, yield strength R el 450-470MPa, tensile strength R m 550-600MPa, elongation A 50 18-20%. While comparative examples 1 to 2 have the same composition as in the examples, but the annealing after the secondary cold rolling is conventionally performed, the temperature is directly raised from room temperature to 980 ℃, the temperature of comparative example 1 is raised faster, and the temperature of comparative example 2 is raised slower, but both result in thicker crystal grains of the product, larger and uneven crystal grain size, and higher iron loss and strength. Comparative example 3, which was the same as the example, was annealed in three steps, but the second step was low in the heating rate, and the proportion of the adverse structure could not be effectively reduced, resulting in a high core loss and a low magnetic induction. Comparative example 4, although produced according to the process of the present application, does not contain Sn element, resulting in lower magnetic induction; in comparative example 4, sn was added, but Ce was not contained, and the crystal grains could not be properly coarsened, resulting in a significant increase in iron loss of the product.
Claims (10)
1. The non-oriented electrical steel for the new energy automobile driving motor is characterized by comprising the following components in percentage by mass:
c:0.001-0.005%, si:3.2-3.5%, mn:0.35-0.65%, al:0.50-0.80%, P: less than or equal to 0.02 percent, S: less than or equal to 0.005%, less than or equal to 0.010% and less than or equal to 0.020% of Ce+Sn, and the balance of iron and unavoidable impurities.
2. The non-oriented electrical steel for a new energy automobile driving motor according to claim 1, wherein the composition of the non-oriented electrical steel for a new energy automobile driving motor further satisfies: ce/sn=0.25-2.0.
3. The non-oriented electrical steel for a new energy automobile driving motor according to claim 1 or 2, wherein the structure of the non-oriented electrical steel for a new energy automobile driving motor has a grain size of 70-120 μm; the product performance is B 50 ＝1.69-1.72T，W 1.0/400 11.0-12.2W/Kg, yield strength R el 450-470MPa, tensile strength R m 550-600MPa, elongation A 50 18-20％。
4. A method for manufacturing the non-oriented electrical steel for a new energy automobile driving motor according to any one of claims 1 to 3, characterized by comprising: smelting, heating a plate blank, hot rolling, coiling, normalizing, pickling, first cold rolling, intermediate annealing, second cold rolling and annealing.
5. The method according to claim 4, wherein the hot rolling is performed, the thickness of the hot plate is controlled to be 1.8mm-2.4mm, the hot rolling is performed, the heat preservation is performed at 500 ℃ to 700 ℃ for 0.1h to 10h, and the hot rolling is performed and then the hot rolling is cooled in a protective gas; the protective gas is N with the volume ratio of 50-100% 2 And 0-50% H 2 。
6. The method of manufacturing according to claim 5, wherein the first cold rolling is performed with a reduction of 50% to 85%.
7. The method according to claim 5, wherein the intermediate annealing is performed at an annealing temperature of 800 to 950 ℃.
8. The manufacturing method according to claim 5 or 7, characterized in that the intermediate annealing is specifically: heating the slab subjected to the first cold rolling to 800-950 ℃ at a heating rate of more than or equal to 100 ℃/s, and then preserving heat for 20-60 s; the volume content of hydrogen in the atmosphere of the annealing furnace is controlled to be more than or equal to 30 percent, the balance is nitrogen, and the grain size after annealing is controlled to be 70-90 mu m.
9. The method of manufacturing according to claim 5, wherein the second cold rolling is performed to a target thickness; the second cold rolling adopts three times of rolling, and the first pass reduction rate is more than 35%.
10. The method of manufacturing according to claim 5, wherein the annealing is performed in three stages;
the first section: raising the temperature from room temperature to 400-600 ℃;
and a second section: raising the temperature from 400-600 ℃ to 910-950 ℃ and controlling the temperature raising rate to be more than 200 ℃/s;
third section: the temperature is raised from 910 ℃ to 950 ℃ to 980 ℃ to 1050 ℃, the temperature raising rate is controlled below 100 ℃ per second, and the heat preservation time is 5s to 30s.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| WO2024172095A1 (en) * | 2023-02-15 | 2024-08-22 | 日本製鉄株式会社 | Non-oriented electromagnetic steel sheet and method for manufacturing same |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| WO2024172095A1 (en) * | 2023-02-15 | 2024-08-22 | 日本製鉄株式会社 | Non-oriented electromagnetic steel sheet and method for manufacturing same |
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