TW200403346A - Nonoriented magnetic steel sheet, member for rotary machine and rotary machine - Google Patents

Abstract

This invention provides a nonoriented magnetic steel sheet which has a chemical composition in mass% in which contents of Si and Mn are 0.1 to 1.2% and 0.005 to 0.30%, respectively, and the contents of C, Sol.Al and N are limited to 0.0050% or less, 0.0004% or less, and 0.0030% or less, respectively, all including 0%, and has a number density of grain growth inhibiting ductile non-metallic inclusions dispersed in the steel sheet of 1000 pieces/cm2 or less including 0, in which a grain growth inhibiting ductile non-metallic inclusion means an inclusion contained in a steel sheet having been subjected to finishing annealing which has a length of 3 x D to 9 x D, D representing an average particle diameter of re-crystallized grains in the steel sheet. The nonoriented magnetic steel sheet allows the production, from one steel sheet, of a rotor material exhibiting a high magnetic flux density and a high strength and a stator material exhibiting a high magnetic flux density and a low iron loss after it is subjected to strain removing annealing.

Description

(1) (1) 200403346 发明 Description of the invention [Technical field to which the invention belongs] The present invention relates to a non-oriented electromagnetic steel plate used for assembling a rotating machine ° The present invention also relates to a member for a rotating machine assembled using the above non-oriented electromagnetic steel plate As well as spinning machines. [Previous technology] To reduce the energy waste of the rotating machine, increase the magnetic flux density of the iron core of the rotating machine, that is, the rotor (Rotes) and the stator (Stator), and try to reduce the iron loss of these iron cores. effective. In order to reduce the iron loss, it is generally a means to increase the resistance of the core material by increasing the content of Si, A1, Mn, and the like. In addition to these methods, the method of adding B as disclosed in Japanese Patent Laid-Open No. 5 8-1 5 1 4 5 3 and the method disclosed in Japanese Patent Laid-Open No. 3-2 8 1 75 8 are known. How to add Ni, etc. In addition, there is a proposal to improve the magnetic properties by combining the structure of an electromagnetic steel plate, for example, by promoting the preferential growth of crystal grains with a {100} <UVW> orientation. . That is, by using non-oriented electromagnetic steel sheets manufactured by these methods, iron cores with high magnetic flux density and low iron loss can be manufactured. However, the non-oriented electromagnetic steel sheet used in the core of the rotating machine is the final refined annealing (final annealing) applied by the steel plate manufacturer to produce the product. After the plate is shipped, it is assembled by the needy into the rotor and stator of the rotating machine. In this assembly process, a steel core plate for a rotor or a core plate for a stator is punched from a steel sheet, and then strain annealed as necessary. -5- (2) (2) 200403346 There are also proposals to improve the growth of recrystallized grains during the strain annealing to obtain more excellent low iron loss technology. For example, in JP 5-8-5 2 210 and JP 8-269532, it is disclosed that the amount of Sol.Al in the steel sheet is reduced to 0.0010% or less and 0.003% or less, respectively, by suppressing fine A1N Precipitation to improve grain growth during strain annealing, and to obtain a low iron loss technology. Also, Japanese Unexamined Patent Publication No. 3-2 4 2 2 9 also discloses that the amount of Sol.Al can be reduced to less than 0.001%, and the grain growth performance during strain annealing can be improved by suppressing the content product of N and v below a predetermined threshold. To obtain low iron loss technology. Japanese Unexamined Patent Publication No. 7-7 0 7 1 9 discloses a method for improving the grain growth property during strain annealing by reducing the amount of Sol.Al to 8 ppm or less and controlling the amount of Ti + Al to 20 ppm or less. . In JP-A No. 63 — 1 952 1 7 or JP-A No. 7-1 50248, it was also disclosed that the composition of inclusions formed by reducing the Al content and controlling the complex oxides of Si, A1, and Mη was Preventing the ductility of the inclusions can improve the grain growth properties during strain annealing and achieve low iron loss. However, although the iron loss improvement in strain annealing is not sufficient with these techniques, for example, after final annealing (at the time of shipment), a steel sheet of about 6 W / kg may be improved to less than about 5 W / kg by strain annealing. However, it is very difficult to improve the steel sheet after the final refining annealing (at the time of shipment) to about 5W / kg by strain annealing to improve it to less than about 4.4W / kg. P. In the case of iron cores for gas-rotation machines, in order to maintain the high quality of the material, it is the same as that of the core material. Μ The core plate for the rotor is punched from the same steel plate by a punching machine. The core plate for the stator and the stator is divided into -6- (3) 200403346. Do not stack the rotor and the stator. Among them, the rotor is a rotating member, and it is required to have local strength due to high-speed rotation stress'. Especially in recent years, in order to improve the efficiency of the (motor), the rotor phase of the rotor-embedded rare-earth magnet method has significantly increased the rotation speed. Therefore, the magnetic flux density and strength, such as the rising and falling points (YP) of constituent steel plates are higher than conventional ones. In addition, it is important that the stator has high magnetic flux density and low iron loss in order to reduce the size of the rotating machine. In this way, although it is the electromagnetic steel plate used in the same motor, the required characteristics of the combined steel plate (hereinafter referred to as "rotor material") and the assembled stator plate (hereinafter referred to as "stator material") make the two characteristics coexist. It is difficult because the conventionally proposed technology can meet the characteristics of a rotor material or a stator material, but it can meet the characteristics of both parties. SUMMARY OF THE INVENTION The object of the present invention is to provide a material and a stator material from the same steel plate. In order to obtain a high non-directional electromagnetic steel sheet that can achieve high magnetic flux strength for the rotor material and high magnetic flux density and low iron loss for the stator material, it also provides a rotating machine member and a rotating machine using the above-mentioned non-directional plate. The invention is: 1. It contains Si: 0.1% ~ 1.2% and Mn: 0.30% by mass ratio, and is limited to c: 0.0050% or less (including 0), which is susceptible to local high-rotation machines. Development, the electromagnetic of the child) is required to be able to be equipped with a rotor to make the steel used differently, although some are not shaped to take the rotor density and high magnetic flux density electromagnetic steel 0.005 ~ Sol.Al: (4) (4 200403346 0.0004% or less (including 0), N: 0.0030% (including 0), and the remainder (the rest) contains Fe and unavoidable impurities, and the steel sheet is dispersed and prevents the growth of ductile non-metallic inclusions (deforMable non — Metallic inclusion with grain growth inhibition) A high magnetic flux density non-directional electromagnetic steel sheet for a rotating machine with a number density (nuMber of inclusion per unit area) of 1,000 pieces / cm2 or less (inclusive). Here, ductile non-metallic inclusions that inhibit grain growth refer to inclusions with a length of 3xD to 9xD assuming that the average recrystallized grain size (average grain size of recrystallized grains) of the steel sheet of ductile nonmetallic inclusions is D . Here, the steel sheet refers to the state of the final refined and annealed product sheet, that is, the state without strain annealing. Of course, the average recrystallized grain size and the length of the ductile non-metallic inclusions are still in the state of the product sheet.値. In addition, although ductile non-metallic inclusions refer to coarser non-metallic inclusions that are easier to extend (or extend in product plates, etc.) by rolling, they are only called non-metallic inclusions in the case of steel plate elongation, so they are only referred to hereinafter as non-metallic inclusions. Ductile inclusions. The composition of the non-oriented electrical steel sheet is preferably substantially composed of Si, Mn, Sol. Al, N, residual Fe, and unavoidable impurities. 2. In the case of conversion by mass%, one or two of Sb: 0.005% to 0.10% and Sn: 0.005% to 0.2% are selected. The high magnetic flux density for a rotary machine related to the invention of item 1 above is not included. Directional electromagnetic steel plate. 3. When it is converted to mass%, it contains one or two selected from P: 0.001% to 0.2% and Ni: 0.001% to 0.2%, which is the same as the above 1 or -8- (5) (5) 200403346 2 The invention relates to a high magnetic flux density non-oriented electrical steel sheet for a rotating machine. 4. When it is converted into mass%, it is one of the REM: 0.0001% to 0.10% and Ca: 0.0001% to 0.01%, or a rain type, which is related to any one of the above inventions 1 to 3, Non-directional magnetic steel sheet with magnetic flux density. 5. When Ti, Nb and V in the above unavoidable impurities are converted by mass%, they are limited to Ti: 0.0020% or less (including 0), Nb: 0.0050% or less (including 0), and V: 0.0060% or less ( Including 0), the high magnetic flux density non-oriented electrical steel sheet for a rotating machine according to any one of the inventions 1 to 4 above. 6. When S and O in the above-mentioned unavoidable impurities are converted by mass%, they are respectively limited to S: 0.0050% or less (including 0), and 0: 0.0100% or less (including 0) and any of 1 to 5 above. The invention relates to a high magnetic flux density non-oriented electrical steel sheet for a rotating machine. 7. The high-density non-oriented electromagnetic steel sheet for a rotating machine according to any one of the above-mentioned inventions 1 to 6 having an average particle diameter D of the recrystallized grains of 6 // M to 25 // M. 8. At least steel sheet manufactured by cold rolling and subsequent final refining and annealing, and the temperature of the above final refining and annealing is 700 ° C ~ 800 ° C, and the high magnetic field for a rotary machine according to any of the above inventions 1 to 7 Flux-free non-oriented electromagnetic steel sheet. That is, a flat steel blank for a non-oriented electrical steel sheet is subjected to a conventional treatment to form a cold-rolled steel sheet having a final sheet thickness, and then a final refined and annealed at 70 ° C to 800 ° C. 9. Any one of the above 1 to 8 The non-directional electromagnetic steel of the invention-9- (6) 200403346 The plate was annealed at 750 ° C for two hours of strain annealing, and the average re-growth was more than twice (that is, the characteristic of the strain annealing crystal grain growth ratio is 2) High magnetic flux density non-oriented electromagnetic steel sheet for rotating machines. 10. Strain annealing high magnetic flux density for rotary machines by applying strain to the non-directional magnetic steel sheet (product plate) of rotary machine flux density related to any of the inventions 1 to 9 above. Non-oriented electrical steel sheet (strain annealing 11 · The temperature of the above-mentioned strain annealing is 700 ° C ~ 800. (: 10) The non-directional high magnetic flux density non-directional plate for a rotating machine according to the invention of 10. That is, the same as the above 1 ~ 9 The non-oriented sheet related to each invention can also be set as follows: After processing the flat steel blank for non-oriented electromagnetic steel sheet to form a cold-rolled steel sheet with a final thickness, apply final finishing annealing at 700 ° C- Apply at 7 0 ° C ~ 80 0 ° C It is better to make the average recrystallized grain size grow more than the size after final refining and annealing. 12. It is preferable that the density non-oriented electrical steel sheet for a rotating machine according to any one of the inventions 1 to 9 above is punched The rotor member for a rotating machine is then completed. 1 3 · The density non-oriented electrical steel sheet for a rotating machine according to any one of the inventions 1 to 9 above is preferably formed by punching and laminating and applying strain annealing. Stator member for rotating machine. 14. Rotating machine having the rotor member related to the invention of the above 12 using the same local magnetic flux density non-directional plate for the rotating machine as the raw material and the stator member related to the above. It is a plate made of high magnetism.) The two-layer magnetic flux stacking with 5 strain passes is used to pass the above-mentioned -8 00 ° C strain relief, and then the electromagnetic steel 13 is issued. • 10- (7 (7) 200403346 That is, the non-oriented electrical steel sheet according to the inventions of 1 to 9 above can be punched and then laminated to form a high-strength rotating machine rotor member. It can also be punched and laminated. Strain annealed It can be used as the stator member of the rotating machine with low iron loss. Moreover, the rotor member and the stator member obtained from the high magnetic flux density non-oriented electromagnetic steel plate for the same rotating machine can also be used to obtain a high-performance rotating machine. First focus on the following points: (1) The saturation magnetic flux density of non-oriented electromagnetic steel plates is determined by the iron content (mass%) of the raw material. When the content of elements other than iron, such as Si or Mn, is high, it cannot be avoided. Decrease in saturation magnetic flux density. (2) The magnetic flux density and strength are governed by the crystal grain size of the steel sheet. (3) If necessary, strain annealing is performed as required, because the crystal grain size may increase and the annealing may occur. Reduction of iron loss. Taking the above results into consideration, the present inventors have discovered that the following methods are combined. (1) By using non-oriented electromagnetic steel sheet with low Si content and Mn content to ensure high magnetic flux density; (2) The final refined and annealed product sheet is finer and higher strength, and it can ensure the strain annealing High growth of crystal grains; (3) Strain annealing is not performed on the rotor material to ensure strength, and strain annealing is applied to the stator material to achieve low iron loss by grain growth; by using the above combination, the crystal grain size can be within the above range. Rotor and stator manufacturing-11-(8) (8) 200403346 The manufacturing process is appropriately optimized to give the rotor and stator the required characteristics, respectively. The present inventors have further explored the main reason for controlling the growth of crystal grain size in the strain annealing process performed in the stator assembly process, and have found that the following methods are combined. (1) Limit the upper limit of A1 to a rather severe industrial level to suppress fine precipitates such as A1N; (2) The number density of ductile inclusions dispersed in the steel plate and the average of the steel plate that is finally refined and annealed The relationship between the crystal grain size is limited to the specified value, that is, it is found that ductile inclusions in a specific size range dominate the grain growth during strain annealing, and can achieve more dense and effective control of ductile inclusions. The above combination, the strain annealing process (for example, at about 700 ° C for two hours) during the stator assembly process of the consumer can make the crystal grain size grow remarkably, so as to achieve the cost of invention. Hereinafter, a more suitable chemical composition (mass%) of the electromagnetic steel sheet of the present invention will be described in detail.

Si: 0.1 to 1.2% To increase the electrical resistance of the steel sheet and reduce iron loss, it is necessary to contain at least 0.1% Si. However, if the Si content exceeds 1.2%, the magnetic flux density decreases and the hardness increases, further deteriorating the workability. Therefore, the Si content is set to a range of 0.1 to 1.2%. Mn: 0.005 to 0.30% Mn is a component required to obtain good workability at the time of hot rolling. Therefore, it must contain 0.005% or more. However, if it exceeds 0.30%, the magnetic flux density -12- (9) 200403346 degrees will decrease. Therefore, the Mη content is set to 0.005 to 0.30% C: 0.0050% or less (including 0). C must be kept as low as possible in order to suppress magnetic aging deterioration. In addition, under the conditions of extremely low A1, the improvement effect of the combined structure needs to be reduced to 0.0050% or less. However, such C does not necessarily need to be at the stage of molten steel or flat steel billet of the starting material. In other words, it is only necessary to finish the finish refining annealing in the steel sheet manufacturing process. A typical decarburization method is decarburization annealing. In the decarburization process, the C content of the starting material is preferably 0.0050% to 0.1%.

Sol.Al: 0.0004% or less (including 〇) In order to obtain excellent grain growth and magnetic properties, the A1 of the steel sheet should be reduced to 0.0004% or less. If the content of A1 exceeds 0.0004%, A1N is precipitated, and the magnetic flux of the final refined and annealed product plate is reduced. In addition, the growth of recrystallized grains during strain annealing is also reduced, and the superior effect of the present invention that can significantly reduce the amount of iron loss. N: 0.0030% or less (including 0) N causes precipitation of nitrides (A1N) in combination with A1 and causes the formation of various nitrides in combination with Ti, which contributes to a decrease in the magnetic flux density of the final fired product. In addition, the growth of the crystal grains in the strain annealing is hindered, which causes the iron drop to be sufficiently reduced. The content demand is reduced to less than 0.0030%. It is preferably 0.0025% of the non-oriented electrical steel sheet according to the present invention. In addition to the above, the steel sheet characteristics corresponding to the purpose can also be added with S b, S η, P, N i. When the content is within the range, the density of the steel plate cannot be obtained, and the refining time is also N. Composition REM, -13- (10) (10) 200403346

At least any one of Ca. The preferred content of these will be described later. In addition to the above, if at least one of Cr: 5% or less and Cu: 5% or less is contained, the effect of the present invention is not hindered. In addition, other representative unavoidable impurities are Ti, Nb, V, S, and 0, and a more appropriate range of these will be described later. In addition, unavoidable impurities such as Cu: 0.2% or less, Cr: 0.08% or less, Zr: 〇 · 〇〇5% or less, As: 0.01% or less, Mo: 0.005% or less, W: 0.005% or less . Although the non-oriented electrical steel sheet of the present invention has the above basic composition, the control of the composition alone cannot achieve the purpose of the present invention. When the average recrystallized grain size of the steel sheet (finished and annealed product sheet) is dispersed in the non-metallic inclusions dispersed in the final refined and annealed steel sheet, the length is 3 XD ~ 9 XD ductile inclusions (ductility) The number density of non-metallic inclusions) needs to be 10000 pieces / cm2 or less (including 0). In the future, ductile non-metallic inclusions having a length of 3 X D to 9 X D will be defined as ductile non-metallic inclusions that hinder grain growth. Here, the average recrystallized grain size is determined by measuring the number of crystal grains existing in the area of 0.5 cm2 of the steel sheet, and calculating the average area of each crystal grain based on it, and then calculating the diameter of a circle having the same average area, and using The diameter. This average recrystallized grain size can be measured by observing the cross-section (so-called L-section) of the steel sheet which is cut perpendicular to the web direction. Ductile inclusions are rod-shaped inclusions that extend in the rolling direction and inclusions that are continuously arranged in the rolling direction. In addition, the inclusions at a distance of 2 or more within 1 〇 / Μ are aligned along the rolling direction within ± 5 °. -14- (11) (11) 200403346, the inclusions are regarded as connected 'Look at it as a ductile inclusion. In addition to the ductile inclusions described above, the inclusions have isolated circular inclusions. This is not a ductile inclusion 'and it is not a ductile inclusion. In addition, the inclusions are classified as round when the major diameter is less than twice the minor diameter, and those which are more than twice as ductile are classified as ductile inclusions. Typical ductile inclusions include S i 0 2, A 1 2 0 3, M n 0, C a 0, or some of these composite oxides (but sometimes they become non-ductile due to their composition). The length of ductile inclusions refers to the maximum length of the line drawn between the bottom iron (parent structure) and any two points on the inclusion interface, that is, the distance between the ends of the ductile inclusions (this is taken as the long diameter). The measurement of the number of ductile inclusions of a predetermined length is performed in the next step. The cross section of the honing steel plate perpendicular to the width direction of the honing steel plate was observed with an optical microscope to observe the original honing surface (without uranium-corrosion treatment), and the small area different from the color of the bottom iron was identified as ductile inclusions. Set the observation field of view to 5mm2 for one sample. Calculate the number of ductile inclusions of a given length that can be considered as the inclusions identified above, and convert the number per 1 cm2 from the number to determine the number density. . The following shows the results of experiments conducted to investigate the effect of grain growth on ductile inclusions. (Experiment 1) With C: 0.002%, Si: 0.7%, Mη: 0.2%, Sol · A1: 0.0004% or less, S: 0.002%, the inevitable (12) (12) 200403346 impurities of the remainder (the rest) are The basic component is manufactured from a flat steel blank that varies from 0.0010 to 0.00 60% of the basic component N. The obtained flat steel slab was heated to 100 ° C and hot-rolled to a thickness of 2.3mm, and then pickled, and then cold-rolled to a final thickness of 0.35mm, and then applied at 800 ° C for 15 seconds. The final refined annealing (recrystallization annealing) is performed to make a final refined annealed sheet (product sheet). In addition, the amount of ductile inclusions (number density) and shape (length) are adjusted by, for example: changing the oxygen content and the A1 content to control the amount and composition of oxides; changing the thickness of the flat steel slab, etc. , And change the rolling process during hot rolling to control the amount of inclusions; and so on. In addition, while measuring the average crystal grain size of the obtained product, the inclusions were observed to measure the length and number density of ductile inclusions. The above products were annealed at 750 ° C for two hours (hereinafter referred to as "strain annealing") in an argon (Ar) atmosphere, and the average crystal grain size was measured in the same manner as the final purified annealed plate. The annealing conditions described above are conditions corresponding to strain annealing of the demander. Figure 1 is the ratio of the average grain size of the steel sheet after strain annealing (hereinafter referred to as "strain-annealed crystal grain growth ratio" or "grain growth ratio") to N for the average grain size of the steel sheet after the final refined annealing thus obtained The relationship with the grave is not shown graphically. Here, when the average crystal grain size after final refining and annealing is set to D, the number density of inclusions with a length of 3 XD to 9 XD (called non-metallic inclusions that inhibit grain growth and ductility) is used. mark. • 16- (13) (13) 200403346 It can be seen from Fig. 1 that when the N content is 30 ppm (mass ppm) or less and the number density of ductile non-metallic inclusions that prevent grain growth is less than 1 000 _ γ cm2, the strain The annealing grain growth ratio is 2 or more. However, although the number of ductile non-metallic inclusions that hinder the growth of grains is 1 000 pieces / c m2 with τ, N content exceeding 0.003 0%, or the number density of ductile non-metallic inclusions that hinder the growth of grains exceeds 10%. When the number is 0 / cm2, the crystal grain growth ratio in strain annealing becomes less than 2. (Experiment 2) The same result can be confirmed by the next experiment 2. That is, three flat steel blanks having a thickness of 250 mm formed by the composition shown in Table 1, residual iron, and unavoidable inclusions were manufactured, and the thicknesses of 25 mm, 50 mm, 100 mm, and 200mm sample. After that, the samples were heated to 1070 ° C, and after hot rolling was set to a thickness of 2.5 mm, they were pickled and then cold-rolled to a final thickness of 0.5 mm. Next, the conditions for the final refining annealing (recrystallization annealing) of the continuous annealing type were adjusted to a range of 700 to 800 ° C, and the average recrystallization particle size (referred to as the average crystal particle size in the experimental examples and examples) was set as 1 2 // m or 1 4 // m product board. The resulting product panel was subjected to a strain annealing at 750 ° C for two hours in an Ar atmosphere. The cross sections of these product plates (finally refined annealed plates) and strain annealed plates perpendicular to the web width direction were observed with an optical microscope, and their average crystal grain sizes were measured. In addition, the number density of non-metallic inclusions that inhibit grain growth and ductility was measured on the product sheet. The results are shown in Table 2. As shown in the table, the number of ductile non-metallic inclusions that hinder the grain growth of the product board is dense. -17- (14) (14) 200403346 Samples with a degree of 1 000 / cm2 or less, The growth of strain annealed crystal grains is relatively large. Table 1 Chemical composition of steel number (mass%) C Si Mn Sol.Al N 0 Ti Nb V 1 0.0027 0.50 0.27 0.0003 0.0015 0.0090 0.0003 0.002 0.0010 2 0.0021 0.50 0.23 0.0003 0.0019 0.0085 0.0004 0.002 0.0010 3 0.0026 0.60 0.22 0.0001 0.0018 0.0070 0.0003 0.001 0.0010 -18- (15) 200403346 Table 2 Steel No. Slab Thickness Average Crystal Size Strain Annealing Resistance to Grain Growth Ductility Remarks (mm) Number of non-metallic inclusions in crystal grains after strain annealing before strain annealing (// m) (^ m) Length Specific Density (pcs / cm2) 25 50 4.2 0.3 Invention Example 50 34 2.8 61 Invention Example 1 100 22 1.8 1012 Comparative Example 200 17 1.4 3581 Comparative Example 25 46 3.8 0.7 Invention Example 50 36 3.0 65 Invention Example 2 100 12 26 2.2 811 Invention example 200 19 1.6 2778 Comparative example 25 47 3.9 0.3 Invention example 50 43 3.6 19 Invention example 3 100 26 2.2 286 Invention example 200 22 1.8 1024 Comparative example 25 50 3.7 0.3 Invention example 50 32 2.4 42 Invention Example 1 100 26 2.0 828 Invention Example 200 16 1.2 3731 Comparative Example 25 44 3.1 0.5 Invention Example 50 34 2.4 35 Invention Example 2 100 14 28 2.0 657 Inventive Example 200 22 1.6 2824 Comparative Example 25 50 3.6 0.1 Inventive Example 50 43 3.1 11 Inventive Example 3 100 31 2.2 220 Inventive Example 200 23 1.6 1038 Comparative Example-19- (16) (16) 200403346 The composition is limited by the above, and Properly limiting the number density of ductile non-metallic inclusions that hinder grain growth, the average crystal grain size of the steel sheet after strain annealing (assembled as the core material of the stator) can contribute to the above-mentioned final grain size More than twice. By this, the iron loss of the stator can be greatly reduced. In addition, the rotor is used in a state where it is finally refined and annealed, and its crystal grain size is relatively small, so that it can maintain high strength, especially a high yield point (hereinafter referred to as YP). Furthermore, by using the rotor and the stator, a high-performance rotating machine for high-speed rotation can be efficiently assembled. As for the strength level required for the rotor, as the characteristics of the rotating machine are different, the size of the average crystal grain size that governs the strength of the steel plate can be designed according to the strength level of the required rotor. However, if it is a general rotating machine, the average crystal grain size of the final refining and annealing of the steel plate is preferably 6 to 25 // m. At this time, the strength of the steel sheet is about YP 200 to 400 Mpa, and the Vickers hardness Hv is about 100 to 170. In addition, although the interpretation of the scope of the right to be imparted to the present invention is not affected, the reason why the growth rate of the annealed crystal grains is dominated by the number density of ductile non-metallic inclusions that hinder grain growth can be presumed as follows. First, it is thought that inclusions having the same length as the crystal grain size will most inhibit the grain growth property. Because ductile inclusions exist across one or more crystal grain boundaries, the probability of hindering the growth of the crystal grains is more localized. However, if the total amount of non-metallic inclusions in the electromagnetic steel plate is -20- (17) (17) 200403346, the volume fraction of the steel can be considered to be slightly constant. According to the formula of Zener It is shown that it is less likely that inclusions having extremely long crystal grain sizes will inhibit grain growth. In other words, the extent to which ductile inclusions impede grain growth varies with the length of the inclusions. According to the inventors' knowledge, the length of ductile inclusions is 3 to 9 times the average grain size of the final refined annealed plate. It is the largest when the ductile non-metallic inclusions that hinder the growth of grains. Therefore, due to the number density of ductile inclusions that are long in this range, that is, "ductive non-metallic inclusions that inhibit grain growth", the "strain annealing grain growth ratio" is affected. The Zener formula is the following formula showing the grain growth inhibitory force I of the inhibitor. 1 = (3/4) x (Vxaxp / r0) where V is the molar volume of the parent phase, σ is the grain boundary energy, p is the volume fraction of the precipitate, and r α is the average particle radius of the precipitate. As described above, by controlling the Si, Mn, C, S ο 1.A1 and N contents of the non-oriented electrical steel sheet, respectively, the number density of ductile non-metallic inclusions that prevent grain growth is suppressed to 100%. 〇 / cm2 or less, can increase the strain annealing crystal grain growth ratio, and is made of high magnetic flux density non-oriented electromagnetic steel plate suitable for rotating machines. Furthermore, by limiting the content of Ti, Nb, and V, or adding Sb, Sn, to the composition of the steel sheet, the effect can be further enhanced. This can be confirmed by the following experiments. (Experiment 3) -21-(18) 200403346 Manufactured the ingots of the composition shown in Table 3, the remaining iron, and the unavoidable impurities. After heating these ingots to 10 〇t, they were thickened by hot rolling and acid Washed and cold rolled to a final sheet thickness of 0.5mm. After adding 80 ° C and 10 seconds of final refining and annealing (recrystallization annealing) to the finished product plate, a further 75 ° C and two hours of strain annealing were applied to change the annealing plate. And from the obtained product plate and strain annealing plate parallel to

The same number of samples were punched in each direction and perpendicular to the rolling direction, and the magnetic flux density and iron loss were measured in accordance with JIS. The measurement results are shown in Table 3. The average crystal grain size of each product plate is 10 to 20 // m. The number of ductile non-metallic inclusions that hinder the grain growth of the product board is 1000 pieces / cm2 or less. The material is 2.5mm, and it is made again. It should be rolled into squares C 2 5 5 0 〇, each density is -22- (19) 200403346 Iron loss (W / kg) After strain annealing T— CD 00 LO in CO VII CNJ CNI 00 CO COCO CD CO COCO COCO Strain Annealing before CD CNJ CO Inch CO CO mi OJ LO T— isi CNJ io CO lO CN ιό CNJ ιό CNJ ui 03 EIIIIIII 0.01 I 0.03 0.08 IIIIII ί I 0.01 0.02 I 0.19 &gt; 0.0010 0.0020 0.0065 I 0.0020 0.0020 0.0050 0.0010 0.0010 0.0020! 0.0020 0.0010 0.002 0.006 0.001 0.004 0.002 0.003 0.001 0.002 0.001 0.002 0.001-0.0024 I 0.0006 0.0010 0.0009 0.0015 0.0004 0.0006 0.0005 0.0004 0.0004 0.0004 0.0003 〇0.0065 i 0.0060 I 0.0065 0.0070 0.0060 0.0055 0.0055 0.0055 0.0060 0.0065 _I I 0.0065 iif 2: I 0.0017 0.0022 0.0021 0.0015 0.0020 0.0017 0.0015 0.0022 0.0013 0.0015 0.0024 Sol.AI 0.0001 I 0.0002 | 0.0001 0.0002 0.0001 0.0001 0.0002 0.0001 0.0001 0.0002 I 0.0001 CI | 0.15 0.17 0.16 0.17 0.18 0.17 0.15 0.17 0.17 0.19 0.15 〇5 0.90 0.90 0.90 0.90 0.90 0.90 0.90 0.90 0.90 I 0. 90 j 0.90 〇 0.0018 0.0017 0.0025 0.0019 0.0023 0.0021 0.0018 0.0018 0.0022 0.0024 0.0017 Steel number τ— CM CO inch (D 00 σ &gt;

-23- (20) (20) 200403346 As can be seen from Table 3, by limiting Ti to 0.0020% or less, Nb to 0.0050% or less, and V content to 0.0060% or less, it can promote better magnetic properties after strain annealing. Moreover, by adding one or both of s b or S η, the iron loss after strain annealing can be greatly improved. Although the reason for reducing the amount of Ti, Nb, and V to improve the magnetic properties is not very clear, it can be inferred as follows. Ti, Nb, and V are all elements that form nitrides and carbides. Because of the fine precipitation of these nitrides, similar to the fine precipitation of A1N, it will adversely affect the formation of the combined structure and the growth of the crystal grain size. To. Therefore, it is conceivable that by reducing these elements to prevent the harmful effects mentioned above, good magnetic properties can be obtained.

The effect of reducing the amount of Ti, Nb, and V on the magnetic properties after strain annealing is not clear, but it can be assumed as follows. If the content of Ti, Nb and V is too large, nitrides or carbides will be partially solid-dissolved during annealing of a hot-rolled sheet or recrystallization annealing. In addition, during strain annealing, nitrides or carbides will re-precipitate and hinder the movement of the magnetic wall. Therefore, it is expected that iron loss will be deteriorated when each of the above elements is large. It is also impossible to prevent the precipitation of V and the like to some extent by reducing the V and the like below the above-mentioned preferable range. Therefore, it is conceivable that steels with reduced V or the like can exert the effect of adding s b or S η. Further, it has been known that S b or S η is added to non-oriented electromagnetic steel sheets in order to improve the combined structure and the like to reduce iron loss (for example, Japanese Patent Publication No. 56-54370, Japanese Patent Application Publication No. 2000-129409, and T. Kubota. , T. Nagai; J. Mater. Eng. PerforM. 1 (1 992), p. 2 1 9 etc.). However, in the extreme reduction of A1, n, etc., ductile inclusions are also added. • 24- (21) (21) 200403346 Controlled non-oriented electromagnetic steel sheet, the addition of Sb or Sn can significantly improve the iron loss improvement effect of strain annealing. It is a phenomenon that has not been known before. By limiting the amount of Ti, Nb, and V mixed in the molten iron or Si raw material in the steel in this way, the effect of preventing fine precipitates caused by the reduction of Sol · A1 can be further improved, and at the same time, the magnetic properties can be further improved. In particular, in a component system that minimizes A1, it is advantageous to limit the amount of Ti and Nb plus the amount of v. As a result, the iron loss after strain annealing is particularly large. The limitation of the above-mentioned trace elements is summarized as follows.

Ti: 0.0020% or less (including 〇), Nb: 0.0050% or less (including 〇), and V: 0.0060% or less (including 0)

Ti, Nb, and V systems form fine nitrides or carbides, which hinder the formation of the combined structure and the growth of crystal grains. In particular, according to the present invention, the non-oriented electrical steel sheet, which has a low Sol. A1 and N content, has a particularly significant tendency. When these elements are reduced to Ti: 0.0020% or less, Nb: 0.0050% or less, and V: 0.0060% or less, the tendency to form nitrides or carbides can be suppressed, and the improvement of iron loss after strain annealing is particularly effective. contribution. The preferable addition amounts of Sb and Sn are as follows. From Sb: 0.005 to 0.10% and Sn: 0.005 to 0.2% of the selected one or two

Sb and Sn can suppress the fine precipitation of nitrides, and at the same time, can effectively promote the formation of a magnetically favorable combination structure by reducing the effect of the nitrides on hindering grain growth. Although its effect appears in Sb: 0.005% or more and Sn · 0.005% or more, if it exceeds 0.10% and 0.2%, respectively, it will -25 · (22) (22) 200403346 hinder grain growth. In addition to the above, by limiting or adding the following elements, the characteristics of the steel of the present invention can be more effectively exerted. From P: 0.001 to 0.2% and Ni: 0.001 to 0.2%, one or both of the punching methods will cause a collapse or crushing, or the burrs formed during punching will be too large to reduce the duty factor of the steel sheet. In this case, by adding at least one of P and Ni, the hardness of the electromagnetic steel sheet of the present invention is increased, and these problems can be avoided. Therefore, within the range that does not harm the electromagnetic characteristics, especially the magnetic flux density, these elements can be added according to the requirements of those who need it. From REM: 0.0001 to 0.10% and Ca: 0.0001 to 0.01%. One or two of the selected REM and Ca series have the effect of coarsening sulfide and increasing (ie reducing) iron loss. Therefore, these elements can be appropriately added in a range in which their effects appear, that is, in the range of REM: 0.000 1 to 0.10% and C a: 0 · 0 0 0 1 to 0 · 0 1%. S: 0.0050% or less (including 0), 〇: 0.0100% or less (including 0) If S exceeds 0.0050%, it is combined with Cu or mixed elements (mainly elements mixed with scrap iron and steel scrap) to form MnS or Cu2s. The tendency to become stronger will hinder the growth of crystal grains. Therefore, it is preferable to limit these elements to the above range. The required strength level or iron loss level of non-oriented electromagnetic steel sheet varies with the characteristics of the rotating machine manufactured. Therefore, in the present invention, the final -26- (23) (23) 200403346 refined and annealed steel grain size need not be uniformly determined. However, setting the average recrystallized particle diameter D to 6 to 2 5 &quot; m is advantageous for crystal grain growth ratios, such as 3 or more, which have been annealed with a large strain as described above. The method for manufacturing a non-oriented electrical steel sheet according to the present invention is not particularly limited. It is typically produced by the following method. First, molten iron adjusted to a more suitable composition is formed into a flat steel blank by, for example, a continuous casting method. Then, it was hot-rolled to form a hot-rolled sheet. After hot-rolled sheet annealing is applied as required, cold rolling is applied more than once with intermediate annealing applied, and the final sheet thickness is achieved by finishing. Then, the obtained cold-rolled sheet is subjected to continuous annealing (final finish annealing), and then an insulation coating is applied as required. In addition, if the carbon content of the flat steel slab is more than the component of the present invention, decarburization annealing is appropriately performed after hot rolling. In the present invention, it is important to control the amount and form of ductile inclusions in the inclusions, and in particular, it is important to reduce the length to ductile inclusions whose average crystal grain size is within a predetermined range. That is, the amount of ductile non-metallic inclusions that hinder grain growth is controlled to 1,000 or less / cm2. Such control may be achieved by any one or a combination of the following means. First, there is a means to reduce the absolute amount of non-metallic inclusions in the flat steel blank by reducing the oxygen content. It is also effective to increase the amount of A1 or Mη in non-metallic inclusions in the flat steel billet to make it ductile, or to decrease the amount of A1 or Mη to make it non- ductile (refinement). In addition, by controlling the manufacturing conditions, especially the rolling conditions,

-27- (24) 200403346 The length of metal inclusions can also use ductile inclusions whose final recrystallization annealed steel is less than three times the particle size or more than nine times the size, which can be used to increase or decrease the thickness of the flat steel embryo. Or the thickness of the hot-rolled sheet can be increased or decreased. The lightness of the hot-rolled sheet can adjust the ductile inclusion length of the hot-rolled sheet. The hot rolling rolls are the same, but the length of ductile inclusions can be changed by increasing or decreasing the rolling rate in high temperature areas where inclusions tend to stretch. Moreover, there is a tendency that the accumulated large post-rolling inclusions are longer after hot rolling, and the cumulative rolling rate is smaller, and the delayed intercalation tends to be shorter. The length of things. Conversely, by changing the final refining annealing temperature or soaking time to increase or decrease the average recrystallized particle size, the length of non-metals can be changed from less than three times or more than nine times the average recrystallized particle size. . In the above manufacturing method, the annealing temperature applied to the continuous annealing (final finish annealing) applied to the cold-rolled final cold-rolled sheet is set to ° C to 800 ° C, and the average recrystallization particle size is adjusted to 6 to 25 / / It is good to adjust the hardness of the steel plate to an appropriate level, such as Vickers hardness (Hv) 1 70. Setting the Vickers hardness within the above range is quite suitable from the viewpoint of ensuring strength and punchability. The non-oriented electromagnetic steel plate thus produced can be punched into a rotating iron core, and assembled into a rotor and a stator. At this time, the rotor and the stator core material are cut from the same steel plate, and laminated and assembled as a rotor component, and only the stator component is subjected to strain annealing to promote growth and reduce its iron loss. For rotor core members, plate averaging is not required. For example, the pressure ratio, although the pressure ratio, can also be light pressure ratio debris can also be adjusted than the strip inclusions as the thickness of the main board is 700 m, or 100 ~ steel plate transfer machine with simultaneous punch and fixed grain growth -28- (25) (25) 200403346 It is better to anneal with the strain of grain growth to keep it high strength as it is. Strain annealing is preferably performed in the range of 700 ° C to 800 ° C. The annealing time is preferably about 10 minutes to 3 hours. The conditions for strain annealing are in the above-mentioned range. Although the conditions for strain-annealing the crystal grain growth ratio of 2 or more are more preferable, for example, it is preferably performed at 750 ° C for about two hours in an inert gas atmosphere. In addition, the strain annealing temperature is performed at a temperature higher than the final refining annealing temperature, which is preferable from the viewpoint of ensuring grain growth. In addition, the non-oriented electromagnetic steel sheet that is finally refined and annealed can also be slightly deformed, for example, a rolling deformation of about 0.5 to 5%, and after punching, 700 ° C to 800 is applied. Strain annealing at ° C promotes recrystallization, so that the crystal grain size grows to about 30 ~ 100 # m. The steel plate treated in this way can be used for the assembly of stators that require low iron loss. The preferred strain annealing conditions at this time are also shown in the previous paragraph. (Examples) Hereinafter, embodiments of the present invention will be described more specifically based on examples. (Example 1) A flat steel billet made of a composition of the components shown in Table 4 and the remaining iron (the remaining iron) and unavoidable impurities was manufactured by a continuous casting method. In addition, the amounts of Ti, Nb, V, S, and 0 are reduced below the preferred ranges described above. After heating these flat steel blanks at 110 ° C for 40 minutes, hot rolling was performed to form a 2.5 mm thick hot plate. After the obtained hot-pressed plate was pickled to remove rust, it was cold-rolled and finished into a cold-pressed plate with a thickness of 0.50 mm. Then, in a volume of -29- (26) 200403346, an atmosphere of hydrogen: 50%-nitrogen 50% was applied at 780 ° C, and the final purification annealing was performed. A semi-organic coating solution made of resin and resin was applied to the obtained final refined annealed plate and baked at 300 ° C to form a plate. In addition, the amount (degrees) of ductile non-metallic inclusions that prevent grain growth can be changed by changing the thickness of the flat steel slab or changing the rolling process of hot rolling. From the obtained product sheet, a blank is cut according to JIS C 2550, and the density, iron loss, upper drop point (YP), and Vickers hardness (also, the upper drop point (YP)) are measured in the rolling direction and the vertical direction of rolling. This is also the case. In addition, the average crystal grain size and the number density of ductile inclusions that hinder the growth of the grains were also measured. The measurement was performed perpendicular to the broad direction. Next, the above product plate was subjected to an argon atmosphere in an atmosphere of 7 5 After strain annealing at 0 ° C, the same measurement and average crystal grain size were performed as for the above products, and then the strain annealing crystal grain growth ratio was calculated for 10 seconds: chromate • finished product density: changed • Determination of magnetic Hv). Average non-metallic surface penetration, two small fixed iron losses -30- 200403346 Table 4 Chemical composition of steel number (mass%) Thickness of flat steel blank (mm) C Si Μη Sol.Al N Sb, Sn 21 0.0032 0.75 0.25 0.0003 0.0025 One 200 22 0.0031 0.80 0.25 0.0004 0.0024 One 200 23 0.0031 0.55 0.26 0.0002 0.0021 — 200 24 0.0032 0.75 0.25 0.0002 0.0017 One 280 25 0.0037 0.80 0.27 0.0003 0.0021 — 280 26 0.0028 0.55 0.25 0.0004 0.0022 One 280 27 0.0031 0.55 0.26 0.004 0.0021 Sb: 0.007 200 28 0.0030 0.55 0.24 0.0004 0.0022 Sb: 0.007 280 29 0.0029 0.55 0.25 0.0004 0.0020 Sn: 0.008 200 30 0.0029 0.55 0.24 0.0004 0.0019 Sn: 0.008 280

The obtained results are shown in Table 5. As shown in Tables 4 and 5, those having the composition of the composition according to the present invention and the number density of ductile non-metallic inclusions that hinder the growth of grains have relatively large grain growth during strain annealing, so the iron loss after strain annealing is particularly low. . It is also complementary to the higher yield point (YP) and Vickers hardness (Hv) of the product (in the state of final refined annealing). It is also suitable for punching and manufacturing rotors and stators of rotating machines at the same time. Of course, the magnetic flux density is also sufficiently high. In addition, in the invention examples (27, 2 9) in which Sb or Sn was specifically added, the magnetic improvement by strain annealing was particularly significant. -31-(28) 200403346

Remarks Inventive Examples Inventive Examples Inventive Examples Comparative Examples Comparative Examples Inventive Examples Comparative Examples Inventive Examples Comparative Examples Strain Annealing Crystal Grain Growth Ratio 00 CO CO inch in cvi 00 τ— σ &gt; τ— CD T— 00 inch CD τ— o ub X—Characteristic Bso (T) average grain size after strain annealing (// m) CO CD in S CO CvJ 00 in 00 § s W15 / 50 (W / kg) o inch σ &gt; CO inch inch CO i6 LO in CD CO i〇CO CM LO Slightly ^ nf S ^ _ m 750 583 955 1525 1072 1998 923 I 2004 830 1818 Product characteristics (before strain annealing) Vickers hardness (Hv) 113 110 115 118 115 114 118 118 119 120 &gt; | 298 294 300 295 298 309 309 310 315 τ— x ~ CO average crystal grain size (β rn) CN CO CN t— CM CNI cvj t— CM CM B50 (T) 1.75 1.76 1.76 1.73 1.72 1.72 1.75 j 1.75 i I 1.76 1.74 W15 / 50 (W / kg) ~ · LO uo Buiri 00 l〇o cd CM CD inch iri τ— CD inch to o CD steel number CM CNJ CO CM to CNJ CD CM CNJ 00 Csj 〇 &gt; CNJ -32- (29) (29) 200403346 (Example 2) Manufactured with the composition of Table VI, and the rest is made of residual iron and unavoidable impurities It is a continuous cast flat steel blank with a thickness of 210mm. At this time, the amount of ductile non-metallic inclusions that hinder the growth of the grains is controlled to 1,000 pieces / cm2 or less by slag composition and steel rolling procedures. The obtained flat steel blank was treated in the same manner as in the case of Example 1 to form a product, and tested in the same manner as in the case of Example 1. However, the final refining annealing of steel number 5 8 is performed at 680 ° C, and the final refining annealing of steel number is performed at 850 ° C. The obtained results are shown in Table 7. As shown in Table 7, those who have the composition and average crystal grain size according to the present invention have excellent strain annealing junctions, grain growth ratio, strength, and magnetic properties, thereby becoming suitable for rotors and stators of rotary machines that can be punched and manufactured simultaneously. In addition, it is known that the final refining annealing temperature is particularly controlled to 700 ° C to 800 ° C, or the average recrystallization particle size of the product plate is controlled to 6 to 2 5 &quot; Μ, for high strength before strain annealing The effect of balancing the low iron loss after strain annealing is quite favorable. -33- (30) 200403346 Table 6 Steel number chemical composition (mass%) C Si Mn Sol.Al NS 0 Ti Nb V Other elements 31 0.0039 0.75 0.38 0.0003 0.0027 0.0045 0.0085 0.0004 0.002 0.0020 32 0.0034 0.80 0.25 0.0002 0.0023 0.0030 0.0070 0.0003 0.0003 0.001 0.0020 33 0.0030 0.55 0.20 0.0001 0.0017 0.0025 0.0080 0.0003 0.004 0.0025 34 0.0022 0.30 0.25 0.0001 0.0022 0.0035 0.0080 0.0004 0.003 0.0035 35 0.0045 1.05 0.27 0.0003 0.0015 0.0030 0.0060 0.0005 0.002 0.0025 36 0.0028 0.90 0.25 0.0004 0.0021 0.0040 0.0090 0.0008 0.003 0.0030 37 0.0025 0.35 0.19 0.0003 0.0014 0.0020 0.0060 0.0005 0.004 0.0035 38 0.0023 0.95 0.25 0.0002 0.0018 0.0015 0.0050 0.0004 0.002 0.0030 39 0.0040 1.10 0.27 0.0002 0.0023 0.0013 0.0040 0.0003 0.002 0.0040 40 0.0027 1.10 0.28 0.0001 0.0024 0.0022 0.0070 0.0005 0.004 0.0020 Sb: 0.008 41 0.0020 1.15 0.25 0.0002 0.0021 0.0035 0.0050 0.0004 0.002 0.0040 Sb: 0.061 42 0.0025 0.95 0.26 0.0001 0.0016 0.0040 0.0045 0.0004 0.002 0.0010 SmO.OlO 43 0.0036 0.95 0.20 0.0002 0.0025 0.0035 0.0070 0.0004 0.003 0.0040 Sn: 0.150 44 0.0025 0.60 0.19 0.0001 0.0022 0.0025 0.0075 0.0003 0.003 0.0050 Sb: 0.052, Sn: 0.048, P: 0.080? Ni: 0.050 45 0.0026 0.30 0.11 0.0002 0.0017 0.0022 0.0060 0.0003 0.003 0.0015 P: 0.018 46 0.0038 0.28 0.09 0.0001 0.0029 0.0023 0.0040 0.0004 0.005 0.0015 Ni: 0.22 47 0.0043 0.55 0.25 0.0002 0.0029 0.0020 0.0035 0.0003 0.002 0.0010 P: 0040, Ni: 0.151 48 0.0038 0.75 0.40 0.0003 0.0028 0.0045 0.0080 0.0004 0.002 0.0020 49 0.0033 0.80 0.24 0.0005 0.0023 0.0030 0.0065 0.0004 0.001 0.0020 50 0.0031 0.55 0.18 0.0001 0.0035 0.0025 0.0080 0.0003 0.004 0.0020 51 0.0045 1.05 0.28 0.0003 0.0016 0.0060 0.0065 0.0065 0.0004 0.002 0.0020 52 0.0029 0.90 0.24 0.0004 0.0022 0.0045 0.0110 0.0009 0.003 0.0030 0.002 53 0.0025 0.35 0.21 0.0003 0.0013 0.0019 0.0065 0.0024 0.004 0.0040 54 0.0022 0.95 0.26 0.0002 0.0019 0.0015 0.0050 0.0004 0.006 0.0030 55 0.0040 1.10 0.27 0.0002 0.0022 0.0015 0.0045 0.0004 0.002 0.0060 56 0.0045 1.00 0.24 0.0003 0.0018 0.0060 0.005 0 0.0004 0.002 0.0020 REM: 0.01 57 0.0040 1.05 0.26 0.0003 0.0017 0.0060 0.0040 0.0004 0.002 0.0020 Ca: 0.001 58 0.0040 1.10 0.28 0.0010 0.0080 0.0065 0.0110 0.0004 0.003 0.0060 59 0.0040 1.00 0.23 0.0001 0.0017 0.0015 0.0040 0.0003 0.002 0.0020 60 0.0014 0.60 0.22 0.0001 0.0014 0.0015 0.0015 0.0038 0.0002 0.001 0.0020 Sn: 0.015 P: 0.07 61 0.0026 0.55 0.23 0.0002 0.0015 0.0017 0.0038 0.0002 0.001 0.0020 Sb: 0.01, Ni: 0.10 62 0.0038 0.55 0.20 0.0001 0.0020 0.0015 0.0045 0.0003 0.001 0.0030 Sb: 0.007? Ca: 0.001 , REM: 0.005 63 0.0037 0.65 0.25 0.0001 0.0011 0.0018 0.0050 0.0002 0.001 0.0020 Sn: 0.030, Ca: 0.002 64 0.0022 0.60 0.21 0.0001 0.0018 0.0018 0.0043 0.0003 0.000 0.0010 Sb: 0.035? REM: 0.02 65 0.0025 0.12 0.24 0.0002 0.013 0.0016 0.0051 0.0002 0.001 0.0020 Sb: 0.007, Sn: 0.010 66 0.0010 0.60 0.22 0.0001 0.0021 0.0013 0.0041 0.0002 0.001 0.0020 Sn: 0.015 67 0.0012 0.60 0.19 0.0001 0.0010 0.0019 0.0036 0.0002 0.000 0.0010 Sn: 0.020 -34- (31) 200403346 Before variable annealing) Characteristics of strain annealing after strain annealing Crystal growth ratio W15 / 5O (W / kg) Bso (T) Average crystal grain size (β m) Drop point (MPa) Vickers hardness (Hv) W15 / 50 ( W / kg) Average crystal particle size (β m) 31 53. 1.75 14 292 107 4.1 61 4.5 Invention Example 32 5.4 1.76 15 294 104 4.3 56 3.8 Invention Example 33 5.6 1.76 14 300 106 4.1 61 4.3 Invention Example 34 5.9 1.76 14 295 107 4.7 53 3.8 Invention Example 35 5.2 1.74 14 298 103 4.1 48 3.5 Invention Example 36 5.3 1.75 14 302 104 3.8 55 3.8 Invention Example 37 5.7 1.76 15 292 103 4.8 48 3.2 1 Invention Example 38 5.6 1.74 14 301 107 3.9 48 3.5 Invention Example 39 5.2 1.75 13 294 102 3.8 55: 4.1 Invention Example 40 5.1 1.74 14 298 107 3.6 58 4.1 Invention Example 41 5.1 1.74 13 293 105 3.9 54 4.0 Invention Example 42 5.2 1.75 14 297 108 3.7 59 4.2 Invention Example 43 5.3 1.75 15 295 104 3.9 59 3.9 Invention Example 44 5.5 1.76 15 328 127 3.9 59 3.9 Invention Example 45 5.8 1.76 16 311 123 4.6 50 3.2 Invention Example 46 5.8 1.76 14 305 116 4.5 52 3.6 Invention Example 47 5.9 1.75 13 331 133 4.5 56 4.4 Invention Example 48 6.5 1.72 10 303 108 5 .9 20 1.9 Comparative Example 49 6.8 1.71 10 313 110 6.1 19 1.9 Comparative Example 50 6.9 1.71 10 307 110 6.1 15 1.4 Comparative Example 51 5.8 1.73 11 311 113 4.8 28 2.5 Invention Example 52 5.8 1.73 12 307 114 4.8 30 2.5 Invention Example 53 6.2 1.74 13 305 111 5.1 33 2.5 Invention Example 54 6.0 1.74 13 308 115 4.9 30 2.3 Invention Example 55 5.9 1.73 12 311 109 4.8 25 2.1 Invention Example 56 5.3 1.73 14 297 103 4.2 45 3.2 Invention Example 57 5.4 1.73 13 295 100 4.5 46 3.5 Invention Example 58 8.7 1.76 5 341 132 6.2 14 2.8 Invention Example 59 4.9 1.73 30 272 95 4.4 50 1.7 Invention Example 60 5.4 1.75 14 330 131 3.7 63 4.5 Invention Example 61 5.5 1.74 14 315 120 3.9 59 4.2 Invention Example 62 5.2 1.74 15 295 106 3.7 65 4.3 Invention Example 63 5.2 1.76 14 304 109 3.8 60 4.3 Invention Example 64 5.3 1.75 14 305 107 3.9 58 4.1 Invention Example 65 5.6 1.75 15 301 105 4.0 61 4.1 Invention Example 66 5.2 1.74 14 297 108 3.7 60 4.3 Invention Examples 67 5.2 1.74 14 298 108 3.6 61 4.4 Invention Examples

-35- (32) (32) 200403346 As described above, the present invention can provide a non-oriented electromagnetic steel sheet that is extremely suitable for manufacturing a rotor and a stator for a rotating machine. In addition, the non-oriented electrical steel sheet according to the present invention has not only such characteristics, but also has an excellent so-called recyclability. That is, when a rotating shaft of a motor is conventionally cast with a core material containing a high amount of A1, the surface of the molten iron is oxidized to increase the viscosity. As a result, the filling property of the molten iron mold is reduced, and sometimes a sound casting cannot be obtained. Therefore, it is generally considered that the waste iron slag containing A1 lacks recyclability. However, the non-oriented electromagnetic steel sheet according to the present invention is a low A1 material. The recyclability required for the manufacture is extremely high. Industrial Applicability The high magnetic flux density non-directional electromagnetic steel sheet according to the present invention is capable of simultaneously adopting a rotor material and a stator material from the same steel sheet, and imparting high magnetic flux density and high strength to the rotor material. High magnetic flux density and low iron loss. Thereby, the manufacturing efficiency and output characteristics of the rotating machine member and the rotating machine can be greatly improved. Moreover, the non-oriented electromagnetic steel sheet according to the present invention is also superior to the recyclability during casting, and can improve the castability when the waste iron slag of the punched material is reused. [Schematic description] Figure 1 is the ratio of the grain growth ratio of non-oriented electrical steel sheet, that is, the ratio of the average crystal grain size of the steel sheet after strain annealing to the average crystal grain size of the steel sheet after final annealing and the N content of the steel sheet. The relationship is a graph showing the number of ductile non-metallic inclusions that hinder grain growth as a parameter. -36-

Claims (1)

200403346 Π) Pick up and apply for patent scope 1 · A non-oriented electromagnetic steel plate, characterized by: When converted by mass percentage, it contains: Si: 0.1% ~ 1.2%; MN: 0.005% ~ 0.3%; C: 0.0050 % Or less (including 0); Sol · A1: 0.0004% or less (including 0); N: 0.003 0% or less (including 0); the rest are Fe and unavoidable impurities, relative to the average particle diameter D of the recrystallized grains The number density of inclusions having a length of 3 D to 9 D is 1,000 pieces / cm 2 or less. 2 · If the non-oriented electromagnetic steel sheet of item 1 of the patent application scope, wherein the steel sheet further contains at least one of Sb and SN, when the content is converted by mass percentage, Sb is 0.005% ~ 0.10%; SN is 0.005% ~ 0.2% 〇3 · If the non-oriented electromagnetic steel sheet of the scope of application for the first item, wherein the steel sheet further contains: at least one of P and Ni, the content of which is converted by mass percentage, P is 0.001% ~ 0.2%; Ni is 0.001% to 0.2%. 4. For example, the non-oriented electromagnetic steel sheet of the scope of patent application, the steel sheet further contains: at least one of REM and CA, when the content is converted by mass percentage, REM is 0.0001% ~ 0.10%; CA is 0.0001 %-〇.〇1% 〇5. As for the non-oriented electromagnetic steel sheet in the scope of patent application, the content of -1, Nb, and v in -37- (2) 200403346 is unavoidable. It is limited to Ti being 0.0020% or less (Knowledge 0); Nb is 0.0050% or less (including 0); V is 0.0006% or less (including 0). 6. The non-oriented electrical steel sheet according to item 1 of the patent application, wherein the content of s 〃 and 0 in the unavoidable impurities is limited to S 〇 0.00.0% or less (including 0.005 0% or less (including 0) ) 0) 〇7. For example, the non-oriented electromagnetic steel sheet of 1 gigabyte, wherein the average particle diameter D of the recrystallized grain is ~ 25 &quot; m. 8. The non-oriented electrical steel sheet according to the [application patent scope item], wherein the steel sheet is a steel sheet manufactured by at least cold rolling and subsequent final refining and annealing processes; the above-mentioned final refining and annealing temperature is 700 &lt; t ~ 800 ° C. 9 · The non-oriented electrical steel sheet according to item 1 of the scope of patent application, wherein the steel sheet is annealed at 750 ° C for two hours so that the average grain size of the recrystallized grains is more than doubled. 10. A non-oriented electrical steel sheet characterized by being strain-annealed to a steel sheet as described in any one of claims 1 to 9 of the scope of patent application. 1 1 · The non-oriented electrical steel sheet according to item 10 of the scope of patent application, wherein the temperature of the strain annealing is 70 (TC ~ 800 ° c. 1 2) A rotor member for a rotating machine, characterized in that the rotation The machine rotor member is made by stacking the non-directional electromagnetic steel plates described in any one of the scope of claims 1 to 9. -38- (3) (3) 200403346 1 3. — Rotating Machine A stator member is characterized in that: the stator member for a rotating machine is made by stacking the non-oriented electromagnetic steel plates described in any one of the scope of claims 1 to 9 of the patent application, and then performing strain annealing. 14. A rotating machine, characterized in that the rotating machine has a rotor member for a rotating machine according to item 12 of the patent application scope, and a stator member for a rotating machine according to item 13 of the patent application scope, and the rotating machine Both the rotor member and the stator member for the rotating machine are made of the same non-oriented electromagnetic steel plate.