Non-oriented electrical steel sheet having excellent punching processability, and manufacturing method therefor

Abstract

Disclosed in the present invention is a non-oriented electrical steel sheet having excellent punching processability. The non-oriented electrical steel sheet further comprises the following chemical elements, in percentage by mass: 0<C≤0.0040%, preferably 0.0009-0.0040%; Si: 0.8-2.2%; Mn: 0.05-0.50%; P: 0.005-0.150%; 0<Al≤0.100%, preferably 0.001-0.100%; and Ca+Ce: 0.0003-0.010%, wherein the mass percentages of Si and P satisfy the following condition: the value calculated according to [Si] / (10×[P]) is in the range of 0.53 to 22; and [Si] and [P] respectively represent the numerical values before the percentage sign of the mass percentages of the respective elements. The non-oriented electrical steel sheet and the manufacturing method therefor in the present invention have an appropriate iron loss coefficient and excellent electromagnetic properties, and also have excellent punching processability.

Description

A non-oriented electrical steel sheet with excellent punching performance and its manufacturing method Technical Field

[0001] This invention relates to a steel plate and a method for manufacturing the same, and more particularly to a non-oriented electrical steel plate and a method for manufacturing the same. Background Technology

[0002] For electrical appliances such as motors, compressors, and drive motors, power consumption should be minimized as much as possible. Therefore, when non-oriented electrical steel sheets are used to make electrical cores, they need to have low iron loss, high magnetic induction, and good punching performance.

[0003] Adding large amounts of Si, Mn, and Al alloying elements to steel can significantly reduce the iron loss of non-oriented electrical steel sheets, but it also greatly reduces their magnetic induction. Simultaneously, the mechanical properties of non-oriented electrical steel sheets increase proportionally, deteriorating their punching and processing performance.

[0004] In the prior art, existing patent documents cover the above-mentioned technical fields:

[0005] For example, Chinese patent document CN115404410A, published on November 29, 2022, entitled "A Non-oriented Silicon Steel with Excellent Magnetic Properties After Stress-Relieved Annealing and Its Manufacturing Method," discloses a non-oriented silicon steel with excellent magnetic properties after stress-relieved annealing and its manufacturing method. Without adding precious metals, through reasonable process measures, a non-oriented silicon steel with low iron loss and high magnetic induction with a Si content of less than 1.2% is obtained. Furthermore, after stress-relieved annealing, the product meets the requirements for sheeting processing. However, a shortcoming of the aforementioned patent document is that the steel coil requires a 24-hour aging treatment after annealing, which significantly prolongs the production cycle of the silicon steel.

[0006] For example, Chinese patent document CN114045433A, published on February 15, 2022, entitled "Ultra-low iron loss non-oriented silicon steel and its production method", discloses an ultra-low iron loss non-oriented silicon steel and its production method. The iron loss of the 0.35mm finished product is ≤2.10W / kg. However, the above patent document adopts hot-rolled plate edge trimming + secondary cold rolling treatment, which will increase the cost in the process production. Summary of the Invention

[0007] One of the objectives of this invention is to provide a non-oriented electrical steel sheet with excellent stamping performance. By optimizing its chemical composition design and manufacturing method, the non-oriented electrical steel sheet can obtain a suitable iron loss coefficient and excellent electromagnetic properties, while also possessing good stamping performance.

[0008] To achieve the above objectives, the present invention provides a non-oriented electrical steel sheet with excellent stamping performance, which contains Fe and unavoidable impurities, and also contains the following chemical elements in weight percentage:

[0009] 0 < C ≤ 0.0040%, preferably 0.0009-0.0040%, Si: 0.8-2.2%, Mn: 0.05-0.50%, P: 0.005-0.150%, 0 < Al ≤ 0.100%, preferably 0.001-0.100%, Ca+Ce: 0.0003-0.010%;

[0010] Furthermore, the mass percentage content of Si and P satisfies the following: the value calculated by [Si] / (10×[P]) is 0.53 to 22, where [Si] and [P] are respectively substituted with the values ​​before the percentage signs of the corresponding element mass percentage content. For example, when the Si content is 0.8% and the P content is 0.15%, [Si] / (10×[P]) is 0.8 / (10×1.5) = 0.53.

[0011] Preferably, the non-oriented electrical steel sheet of the present invention has the following chemical elements in weight percentage:

[0012] 0 < C ≤ 0.004%, preferably 0.0009-0.0040%, Si: 0.8-2.2%, Mn: 0.05-0.50%, P: 0.005-0.150%, 0 < Al ≤ 0.100%, preferably 0.001-0.100%, Ca+Ce: 0.0003-0.010%, with the balance being Fe and unavoidable impurities.

[0013] The inventors discovered through research that when Si and P are controlled to have a value of 0.53 to 22 as calculated by [Si] / (10×[P]), it is possible to balance the iron loss, magnetic properties, and punching processability of non-oriented electrical steel sheets.

[0014] In the non-oriented electrical steel sheet with excellent blanking performance described in this invention, the design principles of each chemical element are as follows:

[0015] C: In the non-oriented electrical steel sheet with excellent blanking performance described in this invention, when the C element content is higher than 0.004%, magnetic aging will occur, deteriorating the electromagnetic properties of the steel. Therefore, in the non-oriented electrical steel sheet with excellent blanking performance described in this invention, the mass percentage content of C element is controlled between 0 < C ≤ 0.004%, preferably 0.0009-0.0040%.

[0016] Si: In the non-oriented electrical steel sheet with excellent stamping performance described in this invention, when the Si content is below 0.8%, the strength of the steel cannot be effectively improved; when the Si content is above 2.2%, it leads to a significant reduction in manufacturability. Therefore, in the non-oriented electrical steel sheet with excellent stamping performance described in this invention, the mass percentage of Si is controlled between 0.8% and 2.2%.

[0017] Mn: In the non-oriented electrical steel sheet with excellent blanking performance described in this invention, when the Mn content is below 0.05%, the austenite phase region cannot be effectively expanded; when the Mn content is above 0.50%, it leads to a significant increase in cost. Therefore, in the non-oriented electrical steel sheet with excellent blanking performance described in this invention, the mass percentage of Mn is controlled between 0.05% and 0.50%.

[0018] P: In the non-oriented electrical steel sheet with excellent blanking performance described in this invention, when the P element content is below 0.005%, the blanking performance of the steel cannot be effectively improved; when the P element content is above 0.150%, the cold rolling stability will be significantly reduced. Therefore, in the non-oriented electrical steel sheet with excellent blanking performance described in this invention, the mass percentage content of P element is controlled between 0.005% and 0.150%.

[0019] Al: In the non-oriented electrical steel sheet with excellent stamping performance described in this invention, when the Al content is higher than 0.1%, it significantly reduces the proportion of favorable grain texture and greatly deteriorates the magnetic induction of the steel. Therefore, in the non-oriented electrical steel sheet with excellent stamping performance described in this invention, the mass percentage content of Al is controlled between 0 < Al ≤ 0.1%, preferably 0.001-0.100%.

[0020] Ca+Ce: In the non-oriented electrical steel sheet with excellent blanking performance described in this invention, when the Ca+Ce content is below 0.0003%, it is not conducive to controlling harmful inclusions in the steel; when the Ca+Ce content is above 0.010%, it will reduce the stability of continuous casting. Therefore, in the non-oriented electrical steel sheet with excellent blanking performance described in this invention, the mass percentage content of Ca+Ce is controlled between 0.0003% and 0.010%.

[0021] Preferably, the non-oriented electrical steel sheet of the present invention further contains at least one of the following chemical elements in weight percentage:

[0022] 0 < Ge ≤ 0.0200%, preferably 0.0005 ~ 0.0200%;

[0023] 0 < Bi ≤ 0.01%, preferably 0.0005 ~ 0.0100%.

[0024] Ge: In the non-oriented electrical steel sheet with excellent stamping performance described in this invention, Ge can significantly improve the proportion of favorable crystal texture. When the Ge content exceeds 0.0200%, the manufacturing cost increases substantially. Therefore, in the non-oriented electrical steel sheet with excellent stamping performance described in this invention, the mass percentage content of Ge is controlled to 0 < Ge ≤ 0.0200%, preferably 0.0005 to 0.0200%.

[0025] Bi: In the non-oriented electrical steel sheet with excellent stamping performance described in this invention, Bi can significantly improve the proportion of favorable crystal texture. When the Bi content is higher than 0.0100%, it leads to severe grain refinement. Therefore, in the non-oriented electrical steel sheet with excellent stamping performance described in this invention, the mass percentage content of Bi is controlled to be 0 < Bi ≤ 0.01%, preferably 0.0005 to 0.0100%.

[0026] Preferably, the non-oriented electrical steel sheet of the present invention further contains at least one of Sn and Sb, and the amounts of Sn and Sb, in mass percentage, satisfy the following: Sn: 0-0.20%, preferably 0.01-0.20%; Sb: 0-0.10%, preferably 0.01-0.10%; 0 < Sn + Sb ≤ 0.25%, preferably 0.02-0.25%.

[0027] Sn and Sb: In the non-oriented electrical steel sheet with excellent stamping performance described in this invention, Sn and Sb elements can promote favorable crystal texture growth, improve magnetic induction, and reduce iron loss. Excessive addition of Sn and Sb elements can lead to grain refinement and abnormal segregation. Therefore, in the non-oriented electrical steel sheet with excellent stamping performance described in this invention, it is preferable to control the mass percentage content of Sn element to be greater than 0 to 0.20%, and the mass percentage content of Sb element to be greater than 0 to 0.10%. Furthermore, it is preferable to control the total mass percentage content of Sn and Sb elements to be 0 < Sn + Sb ≤ 0.25%.

[0028] Preferably, in the unavoidable impurities of the non-oriented electrical steel sheet of the present invention, the content of impurity elements satisfies at least one of the following: S≤0.0040%, N≤0.0030%, Ti≤0.0030%.

[0029] In the above technical solution, S, N, and Ti are all impurity elements in steel. When technical conditions permit, to obtain steel with superior performance and better quality, the content of impurity elements in the steel should be reduced as much as possible. Specifically:

[0030] In the non-oriented electrical steel sheet with excellent blanking performance described in this invention, when the sulfur (S) content exceeds 0.0040%, sulfide inclusions are significantly increased, inhibiting grain growth. Therefore, in the non-oriented electrical steel sheet with excellent blanking performance described in this invention, the mass percentage of sulfur is controlled to S ≤ 0.0040%.

[0031] In the non-oriented electrical steel sheet with excellent punching processability described in this invention, when the nitrogen content is higher than 0.0030%, nitride inclusions are significantly increased, inhibiting grain growth. Therefore, in the non-oriented electrical steel sheet with excellent punching processability described in this invention, the mass percentage of nitrogen is controlled to be N≤0.0030%.

[0032] In the non-oriented electrical steel sheet with excellent punching processability described in this invention, when the Ti element content is higher than 0.0030%, nitride inclusions are significantly increased, inhibiting grain size growth. Therefore, in the non-oriented electrical steel sheet with excellent punching processability described in this invention, Ti element is controlled as an impurity, and its content is controlled to be Ti≤0.0030%.

[0033] Preferably, in the non-oriented electrical steel sheet of the present invention, the mass percentage content of Si and P satisfies the following: the value calculated as [Si] / (10×[P]) is 0.67 to 11, preferably 1.56 to 10.5.

[0034] Preferably, the blanking performance index a of the non-oriented electrical steel sheet of the present invention is 0.9 to 25, preferably 0.9 to 8.8, wherein the blanking performance index a is the ratio of the {111} texture strength to the sum of the texture strengths of (100), (110), and (111).

[0035] The inventors discovered through research that (111) the more easily unfavorable textures are generated, the greater the blanking performance index. Controlling the blanking performance index a within the above range can achieve a good yield strength ratio, facilitating subsequent blanking processing of the material.

[0036] Preferably, the thickness of the non-oriented electrical steel sheet of the present invention is 0.35 to 0.5 mm.

[0037] Preferably, the ratio of the yield strength to the tensile strength of the non-oriented electrical steel sheet of the present invention, i.e., Y... S / T S The value (i.e., yield strength ratio) is 67.5 to 74.5.

[0038] The inventors discovered through research that the yield strength ratio of finished steel sheets is closely related to their workability. On the one hand, a lower yield strength ratio is detrimental to blanking because the softer material is prone to burr formation, and the abnormal increase in the shear surface area leads to a decrease in the stacking coefficient, deteriorating the electromagnetic properties of the finished steel sheet. On the other hand, a higher yield strength ratio is also detrimental to blanking because the harder material easily damages the die, resulting in an abnormally reduced die life, and the abnormal increase in the tensile surface area generates shear stress. Furthermore, an excessively high yield strength ratio also deteriorates the electromagnetic properties of the finished steel sheet. Based on this, the present invention limits the yield strength ratio of non-oriented electrical steel sheets to 67.5–74.5.

[0039] Preferably, the iron loss P of the non-oriented electrical steel sheet of the present invention 1.5 / 50 ≤4.0W / kg, magnetic induction B 5000 ≥1.72T.

[0040] In some embodiments, the iron loss P of the non-oriented electrical steel sheet of the present invention 1.5 / 50 The magnetic flux density is 2.8–4.0 W / kg, and the magnetic flux density is B. 5000 It ranges from 1.72 to 1.78 T.

[0041] Another object of the present invention is to provide a method for manufacturing non-oriented electrical steel sheet, which obtains non-oriented electrical steel sheet with excellent punching performance by controlling process parameters.

[0042] To achieve the above objectives, the present invention provides a method for manufacturing non-oriented electrical steel sheets, comprising the following steps:

[0043] (1) Smelting and casting to produce a billet;

[0044] (2) Heating and hot rolling the billet;

[0045] (3) Cold rolling is performed after pickling;

[0046] (4) Continuous annealing: control the soaking time to be 5 to 60 s, and the soaking temperature T = 850 + 11a × {[Si] / (10 × [P])}, where the unit of soaking temperature T is ℃, a represents the punching performance index, and [Si] and [P] are respectively substituted with the values ​​before the percentage sign of the corresponding element mass content.

[0047] The inventors discovered through research that the soaking temperature for continuous annealing is related to the value of [Si] / (10×[P]). When the value of [Si] / (10×[P]) is high, a higher soaking temperature is required to reduce the iron loss of the finished steel sheet.

[0048] In this invention, the blanking performance index is the ratio of crystal texture (111) / [(100)+(110)+(111)], which can be obtained by detecting the crystal textures (100), (110), and (111) in the cold-rolled steel sheet using X-RD (X-ray diffraction). The larger the blanking performance index, the easier it is for the unfavorable texture (111) to be generated. In order to ensure the rapid growth of the favorable textures (100) and (110) in the high-temperature stage after the Curie temperature, the value of a needs to be controlled within the range of 0.9 to 25, and the homogenization temperature needs to be controlled to obtain a good yield strength ratio, which is convenient for the subsequent blanking process of the material.

[0049] Preferably, in step (2) of the manufacturing method of the present invention, the furnace exit temperature of the billet after heating is 1050-1150°C, the final rolling temperature is 800-950°C, and the coiling temperature is 550-800°C.

[0050] Preferably, the manufacturing method of the present invention further includes step (5) after step (4): applying an insulating coating.

[0051] Preferably, in step (1) of the manufacturing method of the present invention, calcium + rare earth treatment is performed during smelting.

[0052] Preferably, in step (2) of the manufacturing method of the present invention, the thickness of the hot-rolled plate is 1.2 to 2.8 mm.

[0053] Preferably, there is no intermediate heat treatment step, such as normalizing, bell-type furnace annealing, heat preservation, or homogenization step, between steps (2) and (3) of the manufacturing method of the present invention.

[0054] The non-oriented electrical steel sheet with excellent blanking performance and its manufacturing method described in this invention have the following advantages and beneficial effects:

[0055] The non-oriented electrical steel sheet with excellent stamping performance and its manufacturing method described in this invention, through optimization of its chemical composition design and process parameters, enables the non-oriented electrical steel sheet to obtain a suitable yield strength ratio while also possessing good electromagnetic properties, thereby obtaining a non-oriented silicon steel sheet with excellent stamping performance. Specifically, the iron loss P of the non-oriented electrical steel sheet with excellent stamping performance described in this invention... 1.5 / 50 ≤4.0W / kg, magnetic induction B 5000 ≥1.72T. Attached Figure Description

[0056] Figure 1 schematically illustrates the relationship between the yield strength ratio and the punching performance index a of the non-oriented electrical steel sheet of the present invention.

[0057] Figure 2 schematically shows the iron loss P during the blanking process of the non-oriented electrical steel sheet with excellent blanking performance corresponding to Example 2 of the present invention and the comparative steel sheet of Comparative Example 2. 1.5 / 50 Differences in degradation effects.

[0058] Figure 3 schematically shows a comparison of the shear surface and tensile fracture surface of the non-oriented electrical steel sheet with excellent blanking performance corresponding to Embodiment 3 of the present invention during the shearing and blanking process. Detailed Implementation

[0059] The following description, in conjunction with the accompanying drawings and specific embodiments, will further explain and illustrate the non-oriented electrical steel sheet with excellent punching performance and its manufacturing method as described in this invention. However, this explanation and illustration do not constitute an undue limitation on the technical solution of this invention.

[0060] Examples 1-9 and Comparative Examples 1-2

[0061] The non-oriented electrical steel sheets with excellent punching performance in Examples 1-9 of this invention are all obtained by the following steps:

[0062] (1) Smelting and casting: The raw materials for steelmaking can be blast furnace iron or high-quality scrap steel, or a combination of blast furnace iron and high-quality scrap steel in a certain proportion. Steelmaking can be carried out by converter steelmaking and continuous casting, or by electric furnace steelmaking and continuous casting. In addition, calcium + rare earth treatment can be carried out to obtain a suitable inclusion control effect.

[0063] (2) Heating and hot rolling: The furnace exit temperature of the billet after heating can be controlled at 1050~1150℃, the final rolling temperature can be controlled at 800~950℃, the coiling temperature can be controlled at 550~800℃, and the thickness of the hot-rolled plate can be controlled at 1.2~2.8mm. Then proceed directly to step (3).

[0064] (3) Cold rolling after pickling: After pickling, cold rolling can be carried out by cold continuous rolling mill or reciprocating rolling mill. The target thickness of cold rolling of non-oriented electrical steel sheet can be controlled to be 0.35-0.50mm.

[0065] (4) Continuous annealing: The soaking time is controlled to be 5 to 60 s, and the soaking temperature T = 850 + 11a × {[Si] / (10 × [P])}, where the unit of soaking temperature T is ℃, a represents the blanking performance index, and its value range is a = 0.9 to 25. [Si] and [P] are respectively substituted with the values ​​before the percentage sign of the corresponding element mass content.

[0066] An insulating coating can be applied as needed after continuous annealing.

[0067] It should be noted that although the comparative steels of Comparative Examples 1-2 were also prepared using the above steps, their chemical composition ratios and process parameters did not meet the design requirements of this invention. Comparative Examples 1 and 2 adopted a conventional continuous annealing process, without designing a soaking temperature based on T = 850 + 11a × {[Si] / (10 × [P])}.

[0068] Tables 1-1 and 1-2 list the mass percentage of each chemical element in the non-oriented electrical steel sheets with excellent punching performance of Examples 1-9 of the present invention and the comparative steels of Comparative Examples 1-2.

[0069] Table 1-1. (wt%, balance Fe and other unavoidable impurities other than S, N, and Ti)

[0070] Table 1-2. (wt%, balance Fe and other unavoidable impurities besides S, N, and Ti)

[0071] Table 2 lists the specific process parameters of the non-oriented electrical steel sheets with excellent punching performance of Examples 1-9 of the present invention and the comparative steels of Comparative Examples 1-2.

[0072] Table 2-1.

[0073] Note: The blanking performance index a is the ratio of the texture strength of {111} to the sum of the texture strengths of (100), (110), and (111), and the formula is a = (111) / [(100) + (110) + (111)]. The crystal texture strengths of (100), (110), and (111) in the cold-rolled steel plate can be obtained by using X-RD (X-ray diffractometer) to detect the crystal texture strengths of (100), (110), and (111).

[0074] Samples were taken from the non-oriented electrical steel sheets with excellent punching performance obtained in Examples 1-9 and the comparative steel sheets in Comparative Examples 1-2. Observations were conducted on the samples of each example and comparative example steel sheet, and various relevant properties were tested. The results of the observations and related performance tests are listed in Table 3. The specific testing methods for the relevant properties are described below:

[0075] Iron loss performance test: Based on the national standard GB / T 3658-1990, the Epstein square circle method was used to test the iron loss performance. The test temperature was 20℃ constant temperature test, the sample size was 30mm×300mm, the target mass was 0.5kg, and the test parameters were P1.5 / 50.

[0076] Magnetic performance testing: Based on national standard GB / T 3658-1990, the Epstein square ring method was used to test iron loss performance. The test temperature was a constant temperature of 20℃, the sample size was 30mm × 300mm, the target mass was 0.5kg, and the test parameter was B. 5000 .

[0077] Mechanical property testing: Based on the national standard GB / T 228.1-2010, yield strength testing was conducted using machined standard specimens at a constant temperature of 20℃. The gauge length for tensile testing was 50mm, and the measurements were performed three times, with the average value calculated. Table 3 lists the relevant performance test results of the non-oriented electrical steel sheets with excellent punching performance in Examples 1-9 of this invention and the comparative steels in Comparative Examples 1-2.

[0078] Table 3.

[0079] As can be seen from Table 3 above, the iron loss P1.5 / 50 of the non-oriented electrical steel sheets in Examples 1-9 are all between 2.8 and 4.0 W / kg, and the magnetic induction B... 5000 All values ​​are between 1.72 and 1.79 T, indicating excellent electromagnetic properties. Furthermore, the yield strength Y of Examples 1-9 is... S Tensile strength T S All values ​​are between 67.5 and 74.5, indicating excellent blanking performance.

[0080] Figure 1 schematically illustrates the relationship between the yield strength ratio and punching performance of the non-oriented electrical steel sheet described in this invention.

[0081] As shown in Figure 1, when the yield strength is low, for example below 67.5, the material is too soft and prone to burr formation. Furthermore, the abnormal increase in the shear surface area leads to a decrease in the stacking coefficient, deteriorating the electromagnetic properties of the finished steel plate, thus hindering punching processes. When the yield strength is high, for example above 74.5, the material is too hard and prone to damaging the die, resulting in an abnormally reduced die life. Additionally, the abnormal increase in the tensile surface area generates shear stress, similarly deteriorating the electromagnetic properties of the finished steel plate, thus hindering punching processes.

[0082] Figure 2 schematically shows the iron loss P during the punching process of the non-oriented electrical steel sheet of Example 2 and the comparative steel sheet of Comparative Example 2 in this invention. 1.5 / 50 Differences in degradation effects.

[0083] As can be seen from Figure 2, as the blanking process continues, the iron loss P in Example 2 and Comparative Example 2 decreases. 1.5 / 50The differences in degradation became increasingly apparent. Example 2 showed an iron loss cracking rate of only about 5% after shearing, while Comparative Example 2 showed an iron loss cracking rate of about 40% after shearing. In Comparative Example 2, the Si content in its composition design was 2.4%, exceeding the design limit of 2.2%, and the Al content was 0.25%, exceeding the design limit of 0.1%. The punching performance index in its process design was 0.48, lower than the design requirement of 0.9 of this invention, thus failing to meet the requirements of this invention. Correspondingly, the yield strength ratio of the obtained comparative steel plate was 76.5, and the iron loss P... 1.5 / 50 It is 4.2W / kg, magnetic induction B 5000 The values ​​are 1.70T, none of which meet the requirements of the invention design.

[0084] Figure 3 schematically shows the shearing surface and tensile fracture surface of the non-oriented electrical steel sheet with excellent punching performance in Embodiment 3 of the present invention during the shearing and punching process.

[0085] As can be seen from Figure 3, in terms of the morphology of the cross-section of the sample in Example 3, the proportion of the shear surface and the tensile surface is roughly the same. The shear surface is very flat and smooth, with a clear boundary with the tensile surface. Consequently, the residual stress of the sample is relatively small, which has a good control effect on the iron loss deterioration of the finished sample.

[0086] It should be noted that the combination of the technical features in this case is not limited to the combination methods described in the claims of this case or the combination methods described in the specific embodiments. All technical features described in this case can be freely combined or combined in any way, unless they contradict each other.

[0087] It should also be noted that the embodiments listed above are merely specific embodiments of the present invention. Obviously, the present invention is not limited to the above embodiments, and similar changes or modifications made thereto are those that can be directly derived or easily conceived by those skilled in the art from the content disclosed in the present invention, and should all fall within the protection scope of the present invention.

Claims

1. A non-oriented electrical steel sheet containing Fe and unavoidable impurities, characterized in that, The non-oriented electrical steel sheet also contains the following chemical elements in percentage by mass: 0 < C ≤ 0.0040%, preferably 0.0009-0.0040%, Si: 0.8-2.2%, Mn: 0.05-0.50%, P: 0.005-0.150%, 0 < Al ≤ 0.100%, preferably 0.001-0.100%, Ca+Ce: 0.0003-0.010%; Furthermore, the mass percentage content of Si and P satisfies the following: the value calculated by [Si] / (10×[P]) is 0.53 to 22, where [Si] and [P] are respectively substituted with the values ​​before the percentage sign of the mass percentage content of the corresponding elements.

2. The non-oriented electrical steel sheet as described in claim 1, characterized in that, The non-oriented electrical steel sheet has the following chemical elements in percentage by mass: 0 < C ≤ 0.004%, preferably 0.0009-0.0040%, Si: 0.8-2.2%, Mn: 0.05-0.50%, P: 0.005-0.150%, 0 < Al ≤ 0.100%, preferably 0.001-0.100%, Ca+Ce: 0.0003-0.010%; the balance is Fe and unavoidable impurities.

3. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The non-oriented electrical steel sheet also contains at least one of the following chemical elements in percentage by mass: 0 < Ge ≤ 0.0200%, preferably 0.0005 ~ 0.0200%; 0 < Bi ≤ 0.0100%, preferably 0.0005 ~ 0.0100%.

4. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The non-oriented electrical steel sheet further contains at least one of Sn and Sb, and the amounts of Sn and Sb, in mass percentage, satisfy the following: Sn: 0-0.20%, preferably 0.01-0.20%; Sb: 0-0.10%, preferably 0.01-0.10%; 0 < Sn + Sb ≤ 0.25%, preferably 0.02-0.25%.

5. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The unavoidable impurities comprise S, N, and Ti, satisfying at least one of the following: S ≤ 0.0040%, N ≤ 0.0030%, and Ti ≤ 0.0030%.

6. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The mass percentage content of Si and P satisfies the following: the value calculated as [Si] / (10×[P]) is 0.67 to 11, preferably 1.56 to 10.

5.

7. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The blanking performance index a of the non-oriented electrical steel sheet is 0.9 to 25, preferably 0.9 to 8.8, wherein the blanking performance index a is the ratio of the {111} texture strength to the sum of the texture strengths of (100), (110), and (111).

8. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The thickness of the non-oriented electrical steel sheet is 0.35 to 0.5 mm.

9. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The ratio of the yield strength to the tensile strength of the non-oriented electrical steel sheet, i.e., Y... S / T S The value ranges from 67.5 to 74.

5.

10. The non-oriented electrical steel sheet as described in claim 1 or 2, characterized in that, The iron loss P of the non-oriented electrical steel sheet 1.5 / 50 ≤4.0W / kg, magnetic induction B 5000 ≥1.72T.

11. The method for manufacturing non-oriented electrical steel sheet according to any one of claims 1-10, characterized in that, The manufacturing method includes the following steps: (1) Smelting and casting to produce a billet; (2) Heating and hot rolling the billet; (3) Cold rolling is performed after pickling; (4) Continuous annealing: control the soaking time to be 5 to 60 s, and the soaking temperature T = 850 + 11a × {[Si] / (10 × [P])}, where [Si] and [P] are respectively substituted with the values ​​before the percentage sign of the corresponding element mass content, the unit of soaking temperature T is ℃, and a represents the punching processing performance index.

12. The manufacturing method as described in claim 11, characterized in that, In step (2), the furnace exit temperature of the billet after heating is 1050-1150℃, the final rolling temperature is 800-950℃, and the coiling temperature is 550-800℃.

13. The manufacturing method as described in claim 11, characterized in that, The method further includes step (5) after step (4): applying an insulating coating.

14. The manufacturing method as described in claim 11, characterized in that, There are no intermediate heat treatment steps, such as normalizing, bell-type furnace annealing, heat preservation, or heat soaking, between steps (2) and (3).

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