TWI276693B - 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/cm<2> 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 3xD to 9xD, 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

1276693 (1) Description of the Invention [Technical Field] The present invention relates to a non-oriented electrical steel sheet for assembling a rotary machine. The present invention also relates to a member for a rotary machine and a rotary machine which are assembled by the above-described non-oriented electrical steel sheet. [Prior Art] When reducing the energy waste of the rotating machine, the magnetic flux density of the iron core of the rotating machine, that is, the rotor (Rotos) and the stator (Stator) is increased, and at the same time, the iron loss of the iron core is equivalent. effective. In order to reduce the iron loss, it is generally a means of increasing the electrical resistance of the core material by increasing the contents of Si, A1, Μη, and the like. Further, in addition to such means, a method of adding ruthenium as disclosed in Japanese Laid-Open Patent Publication No. SHO-58-151541, and Japanese Laid-Open Patent Publication No. Hei. The method of adding Ni, etc. In addition, there is a proposal to increase the magnetic properties by a combination of the structure of the electromagnetic steel sheet, for example, to promote the growth of the crystal grains having the {100} <UVW> orientation, and has been proposed in Japanese Laid-Open Patent Publication No. SHO-58-181822. That is, by using the non-oriented electrical steel sheet manufactured by these means, it is possible to manufacture a core having a high magnetic flux density and a low iron loss. However, the non-oriented electrical steel sheet used for the iron core of the rotating machine is a rotor and a stator which are assembled into a rotating machine by a steel sheet manufacturer after final finishing annealing (final annealing) is applied to the product sheet. In the assembly process, after the core plate for the rotor or the core plate for the stator is punched from the steel sheet, strain annealing is applied as needed. -5- 1276693 . (?) There is also a proposal to improve the recrystallized grain growth property during strain annealing and to further improve the low iron loss. For example, in the Japanese Patent Publication No. Hei. No. 8-269532, and the like, it is disclosed that the amount of steel Sol.Al is reduced to 0.0010% or less and 0.003% or less, respectively, to precipitate fine A1N to improve strain annealing. The technique of producing low iron loss by grain formation. In addition, the amount of Sol·Α1 is reduced to 0.001% or less, and the content of N and v is made below the predetermined enthalpy, and the grain growth during strain annealing is also improved to obtain low iron. Loss technology. Japanese Patent Publication No. 7-7071-9 reduces the amount of Sol.Al to 8 ppm or less, and the amount of Ti+Al to 2 Oppm or less to improve the grain growth property during strain annealing. - 1 9 5 2 1 Bulletin No. 7 or JP-A-7-A, which discloses that the inclusion composition of S i, A1, and composite oxides is controlled by low A1 to prevent the inclusion of the inclusions. It can improve the grain growth during strain annealing, and obtain low iron damage. Although the iron loss of strain annealing is determined by these techniques, for example, 6W / kg left plate after final finishing annealing (when shipped) Strain annealing may be improved to less than 5 W / kg, and the final refining after annealing (when shipped) is reduced to about 5 W / kg. The left plate is strained and annealed to be less than 4.4 W / kg. In the case of "manufacturing a core for a rotating machine, in order to maintain the material rate", a core plate for a core for a rotor is punched from a steel plate by a press machine. Moreover, the iron core plate and the stator are used for the rotor to obtain the -55210 plate, and the length and the length are also revealed, and the exposure is controlled by the method. 150248 Μη的性化, 亦 is not filled with right steel, but the rightmost steel is very difficult to finish the board and the core board -6 - (3) 1276693 Do not stack, and assemble the rotor and stator. Among them, the "rotor is a rotating member, and it is required to have high strength because it is subject to high stress with high-speed rotation". In particular, in recent years, in order to improve the efficiency of the rotating machine (motor), the rotor of the rare earth magnet embedding method has been developed considerably, and the rotational speed of the rotor has remarkably increased. Therefore, the magnetic flux density and strength, for example, the upper drop point (γρ) of the electromagnetic steel sheet constituting the rotor are required to be higher than conventional ones. Further, in order to reduce the size and energy saving of the rotating machine, the stator has high magnetic flux density and low iron loss. In the case of the electromagnetic steel sheets used in the same motor, the steel sheets used for assembling the rotors (hereinafter referred to as "rotor materials") and the steel sheets used for assembling the stators (hereinafter referred to as "stator materials") are different in characteristics. It is quite difficult to coexist two characteristics. Because the technology of the conventional proposal can be individually adapted to the characteristics of the rotor material or the stator material, it is not formed to conform to both characteristics. SUMMARY OF THE INVENTION The object of the present invention is to provide a rotor material and a stator material from the same steel plate to obtain a high magnetic flux density and high strength of the rotor material, and a high magnetic flux density and low iron loss of the stator material. A high magnetic flux density non-oriented electrical steel sheet, and a rotating machine member and a rotating machine using the above non-oriented electrical steel sheet. The present invention is: 1. Containing Si in a mass ratio: 0.1% to 1.2% and Μη: 0.005 to 0.30%, and is limited to C: 0.0050% or less (including 〇), Sol. Al:, (4) 1276693 0.0004% or less (including 〇), N: 0.0030% (including 〇), and containing Fe and the unavoidable impurities in the residue (the rest), and the deforMable non-Metallic inclusion with grain dispersed in the steel sheet The growth inhibition nuMber of inclusion per unit area is a high magnetic flux density non-oriented electrical steel sheet for a rotating machine of 1000 pieces/cm 2 or less (including 0). Here, the obstruction of grain growth ductile non-metallic inclusions means: inclusions having a length of 3xD to 9xD when the average recrystallized grain size of the steel sheet of the ductile non-metallic inclusions (the average particle diameter of the recrystallized grains) is D . Here, the steel plate refers to a steel sheet which is subjected to a final finish annealing of the product sheet, that is, a steel sheet which is not subjected to strain annealing. Of course, the average recrystallized grain size and the length of the ductile non-metallic inclusion are also in the state of the product sheet. After that. Moreover, ductile non-metallic inclusions refer to relatively coarse non-metallic inclusions which are relatively easy to extend by rolling (or extend over a product sheet, etc.), but the steel sheet extension is a non-metallic inclusion, so it will only be referred to hereinafter. Ductile inclusions. Further, the composition of the non-oriented electrical steel sheet is substantially composed of si, Μη, Sol. Al, N, residual Fe, and unavoidable impurities. 2. The rotary machine related to the invention of the above 1 which is one or two selected from the group consisting of Sb: 〇·〇〇5% to 0.10% and Sn: 0.005% to 0.2% in terms of mass % A high magnetic flux density non-directional electrical steel sheet is used. 3. The invention of 1 or 2 selected from the above 1 or (5) 1276693 2 when P: 001.001% 〇 2% and Ni: 0.001% 〜 0.2% in terms of mass % The related magnetic machine has a high magnetic flux density non-directional electrical steel sheet. 4. In addition, in the case of mass % conversion, the rotation of REM: 0·000 1% to 0.10% and Ca: 0.0001% to 0.01%, or the rotation of any one of the above 1 to 3 inventions Machine with high magnetic flux density non-directional electromagnetic steel plate. 5. When the above-mentioned unavoidable impurities Ti, Nb, and V are converted by mass%, they are limited to Ti: 0.0020% or less (including 〇), Nb: 0.0050% or less (including 0), and V: 0.0060% or less ( A high magnetic flux density non-oriented electrical steel sheet for a rotary machine according to any one of the above 1 to 4, which comprises 〇). 6. When the above-mentioned unavoidable impurities S and Ο are converted by mass%, they are limited to S: 0.0050% or less (including 0), and 〇: 0.0100% or less (including 0) and any of the above 1 to 5 The invention relates to a high magnetic flux density non-oriented electrical steel sheet for a rotating machine. 7. The high-flux-density non-oriented electrical steel sheet for a rotating machine according to any one of the above 1 to 6 of the invention, wherein the average particle diameter D of the recrystallized grains is 6/iM to 25//M. 8) a high magnetic material for a rotating machine related to at least one of the above-mentioned inventions 1 to 7 in a steel sheet manufactured by cold rolling and subsequent final annealing annealing, and the temperature of the final finishing annealing is 700 ° C to 800 ° C Passivity non-directional electrical steel sheet. That is, the flat steel blank for the non-oriented electrical steel sheet is subjected to conventional treatment to form a cold-rolled steel sheet having a final thickness, and then finally refined and annealed at 7 〇 〇 〜 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 8 9. Non-directional electromagnetic steel -9-.(6) 1276693 plate-related to any of the above-mentioned inventions 1 to 8 is subjected to strain annealing at 750 ° C for two hours, and the average re-growth growth is more than twice (ie, A high-flux density non-oriented electrical steel sheet for a rotating machine having a strain-annealing crystal grain size growth ratio of 2 is characterized by a rotating machine passivation non-oriented electrical steel sheet relating to any of the above 1 to 9 inventions ( Product plate) High-flux density non-oriented electrical steel sheet for strain annealing annealing machine (strain annealing 11. The above-mentioned strain annealing temperature is 700 ° C to 800 t 1 〇. The high magnetic flux density of the rotating machine is not related. The directional plate, that is, the non-oriented plate of each of the above-mentioned 1 to 9 can also be designed to be formed by processing a flat steel blank for a non-oriented electrical steel sheet to form a cold-rolled steel sheet having a final thickness. It is preferable to apply a final refining annealing at 70 (rc 〃 and apply a fire at 70 to 80 ° C to increase the average recrystallized grain size to be more than the grain size after final refining annealing. The rotary machine according to any one of the above 1 to 9 has no density Preferably, the magnetic steel sheet is subjected to a punching and then a rotor member for a rotating machine. 13. The density non-oriented electrical steel sheet for a rotating machine according to any one of the above 1 to 9 is preferably subjected to die cutting. After laminating, the stator member for a rotating machine is subjected to strain annealing. 1 4. A rotor member according to the above-described 12 invention having a high magnetic flux density non-directional plate for the same rotating machine as a raw material, and a stator related to the above The rotating machine of the component. The crystal grain size is a plate made of high magnetic material.) The high magnetic flux of the two high magnetic flux laminated with the above-mentioned electromagnetic steel electromagnetic steel over the conventional -8 00 °C strain retreat, and then electromagnetic The hair of the steel 13 - (7) 1276693 That is, the non-oriented electrical steel sheets according to the inventions of the above 1 to 9 can be laminated by punching to form a high-strength rotating machine rotor member. The low iron loss rotating machine stator member may be formed by die cutting and laminating and then applying strain annealing. Further, the rotor member and the stator member obtained from the same rotating machine with high magnetic flux density non-oriented electrical steel sheets may be used to obtain High performance rotary machine.

[Embodiment] The present inventors first focused on the following points. (1) The saturation magnetic flux density of the non-oriented electrical steel sheet is determined by the iron content (% by mass) of the raw material. When the content of elements other than iron, such as Si or Μ, is high, the decrease in the saturation magnetic flux density cannot be avoided. (2) The magnetic flux density and strength are governed by the crystal grain size of the steel sheet. (3) If the above-mentioned needer performs strain annealing as needed, the increase in crystal grain size and the decrease in iron loss may occur due to the annealing.

The inventors of the present invention have found that the following methods are combined in consideration of the above results. (1) By using a non-oriented electrical steel sheet with a low Si content and a low Μη content to ensure a high magnetic flux density; (2) a final fine-annealed product sheet having a finer grain and a higher strength, and 'can ensure strain annealing High growth of crystal grains; (3) no strain annealing is performed on the rotor material to ensure strength, strain annealing is applied to the stator material by grain growth to achieve low iron loss; by the combination of the above, the crystal grain size can be Manufacture of rotors and stators -11 - 1276693 . (8) The manufacturing process is adapted to give the rotor and stator the required characteristics. The inventors of the present invention 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) Limiting the upper limit of A1 to a rather severe industrial level to suppress fine precipitates such as A1N; (2) averaging the number density of ductile inclusions dispersed in the steel sheet and the steel sheet being finally refined and annealed The relationship between the crystal grain size and the determined particle size is limited to the predetermined enthalpy, that is, the ductile inclusions in the specific size range are dominantly affected to affect the grain growth during strain annealing, and a more compact and effective ductile inclusion control can be achieved; In the above combination, the strain annealing process (for example, about two hours at 700 ° C) in the stator assembly process of the person in need can make the crystal grain size grow remarkably to achieve the present invention. Hereinafter, the preferred chemical composition (% by mass) of the electromagnetic steel sheet of the present invention will be described in detail.

Si : 0· 1 ～1.2% To increase the resistance of the steel sheet and reduce the iron loss, at least 〇 · 1 % Si is required. However, when the content of Si exceeds 1.2%, the magnetic flux density decreases, and the hardness also rises, which deteriorates workability. Therefore, the Si content is set in the range of from 0.1 to 1.2%. Μη : 0.005 to 0.30% Μη is a component required for obtaining good workability in hot rolling, and therefore needs to be contained in an amount of 0.005% or more. However, if it exceeds 0.30%, the magnetic flux density -12 - 1276693 (?) degree will decrease. Then, the Μη content is set to 0.005 to 0.30% C: 0.0050% or less (including 〇) C is required to suppress magnetic aging deterioration as much as possible. Further, in order to improve the efficiency of the combined structure under the condition of extremely low A 1 , it is necessary to reduce it to 0 · 〇 〇 5 〇 % or less. However, such a C does not necessarily need to be in the stage of the molten steel or flat steel of the starting material. That is, it is sufficient as long as the final refining annealing is completed in the steel sheet manufacturing process. A representative decarburization means is decarburization annealing. Further, it is preferable that the C content of the starting material is 0.0050% to 0.1% at the time of manufacture.

Sol.A1: 0.0004% or less (including 〇) In order to obtain excellent grain growth and magnetic properties, A1 of the steel sheet should be reduced to 0.0004% or less. When the Ai content exceeds 0.0004%, A1N is precipitated, and the magnetic flux of the final refined annealing sheet is lowered. Further, the recrystallized grain growth property at the time of strain annealing is also lowered, and the superior effect of the present invention can remarkably reduce the amount of iron loss. N: 0.0030% or less (including yttrium) N is combined with A1 to form a nitride (A1N). The reason for the formation of various nitrides in combination with Ti or the like causes a decrease in the magnetic flux density of the product which is subjected to the final fire. Further, the strain annealing is inhibited from crystal grain growth, which is a cause of hindering the iron loss to be sufficiently lowered. The content requirement is reduced to 0.003 0% or less. Preferably, the non-oriented electrical steel sheet of the present invention is 0.0025%, and in addition to the above-mentioned base, Sb, Sn, P, and Ni may be added to the characteristics of the steel sheet corresponding to the purpose, and the present invention is sufficiently reduced to achieve a range of progress. The internal content is required, the density of the steel plate is not available, and it is also refined after the retreat. Composition REM, •13- (10) 1276693

At least one of Ca. The preferred contents of these are described later. In addition to the above, if at least one of Cr: 5% or less and Cu: 5% or less is contained, it is not an obstacle to obtain the effect of the present invention. Moreover, Ti, Nb, v, s, and 〇, which are more representative of other unavoidable impurities, are described later in the appropriate range. Further, Cu: 0.2% or less, Cr: 0.08 % or less, Zr: 0.005 % or less, As: 0.01% or less, Mo: 0.005% or less, and W: 0.005% or less are unavoidable impurities. The non-oriented electrical steel sheet of the present invention has the above basic composition, but it is only the control of the composition and the object of the present invention cannot be achieved. When the average recrystallized grain size of the steel sheet (the final refined finish of the product sheet) is assumed to be D, the ductile inclusions having a length of 3 XD to 9 XD (the ductility) in the non-metallic inclusions dispersed in the final refined annealing steel sheet The number density of non-metallic inclusions needs to be 1000 / cm 2 or less (including 〇). The ductile non-metallic inclusions having a length of 3 X D to 9 X D will be defined as hindering grain growth ductile non-metallic inclusions. Here, the average recrystallized particle size is a number of crystal grains present in an area of 0.5 cm 2 of the steel sheet, and the average area of each crystal grain is calculated therefrom, and the diameter of a circle having the same average area is calculated, and the diameter is used. . Such an average recrystallized grain size can be measured by observing a section of the steel sheet which is cut perpendicular to the sheet direction (so-called L section). The ductile inclusions are rod-like inclusions elongated in the rolling direction and inclusions continuously arranged in the rolling direction. In addition, when the inclusions at a distance of more than 2 / 10 / Μ are arranged in the direction of ± 5 ° in the rolling direction - 14 ( . . . 1276693 ) , the inclusions are connected as ' A ductile inclusion is considered. Further, the inclusions have isolated round inclusions in addition to the above-mentioned ductile inclusions. This is not a ductile inclusion, not a ductile inclusion. And the case where the long diameter of the inclusions is less than twice the short diameter is regarded as a circle, and more than two times are classified as ductile inclusions. Representative ductile inclusions, si〇2, A12〇3, MnO, CaO or some of these composite oxides (but sometimes due to composition becoming non-ductile). The length of the ductile inclusion refers to the maximum enthalpy of the scribe line between the bottom iron (parent phase structure) and any two points of the inclusion interface, that is, the distance between the ends of the ductile inclusion (this is taken as the long diameter). The determination of the number of ductile inclusions of a predetermined length is carried out in the next step. A section perpendicular to the width direction of the steel plate is honed, and the surface of the honing (without etching treatment) is observed by an optical microscope, and a small area different from the color of the bottom iron portion is identified as a ductile inclusion. The observation field of view is set to 5 mm 2 for one sample, and the number of the ductile inclusions in the above-mentioned identified inclusions is considered to be the number of the objects, and the number per 1 cm 2 is converted from the number of the samples as the number density. . Hereinafter, the experiment and the results of investigating the influence on the grain growth of the ductile inclusions are shown. (Experiment 1) C ·· 0.002 %, Si : 0.7 %, Μη : 〇·2 %, Sol.A1 ·· 0.0004% or less, S: 0.002%, inevitable -15- of the residue (the rest) (12 1276693 Impurity is an essential component, and a flat steel embryo is produced in which the basic component N varies from 〇.〇〇10 to 0.0060%. The obtained flat steel embryo is heated to ll 〇〇 ° C and hot rolled to a thickness of 2.3 mm, then pickled, and then cold-rolled and finished to a final thickness of 〇 35 mm, and then applied again at 80 ° C, 1 Final finishing annealing (recrystallization annealing) was carried out for 5 seconds to prepare a final refined annealing sheet (product sheet). Further, the amount of the ductile inclusions (number density) and the shape (length) are adjusted by, for example, changing the oxygen content and the A1 content to control the amount and composition of the oxide; changing the thickness of the flat steel embryo, etc. And changing the rolling process during hot rolling to control the amount of inclusions; etc.; Further, the obtained product was measured for the average crystal grain size, and the inclusions were observed to measure the length and the number density of the ductile inclusions. The product was subjected to annealing at 750 ° C for two hours in an M (Ar) atmosphere (hereinafter referred to as "strain annealing"), and the average crystal grain size was measured in the same manner as in the final fine-annealed sheet. Further, the above annealing conditions are conditions equivalent to strain annealing of a person in need. Fig. 1 is a ratio of the average crystal grain size of the steel sheet after strain annealing of the average crystal grain size of the steel sheet after the final finish annealing thus obtained (hereinafter referred to as "strain annealing crystal grain growth ratio" or "grain growth ratio") and N The relationship between the contents shows the chart. Here, the number density of inclusions having a length of 3 XD to 9 XD (referred to as a grain growth ductility non-metallic inclusion) is used in the case where the average crystal grain size after the final finish annealing is D, and the use is different. mark. -16- (13) 1276693 It can be seen from Fig. 1 that the N content is 30 ppm (mass ppm) or less, and the grain growth retardation non-metallic inclusions have a number density such as 10 〇〇 _ / cm 2 or less, strain annealing crystallization The grain growth ratio is 2 or more. However, when the grain growth ductility non-metallic inclusions are less than 1 000 /cm2, the N content is more than 0.0030%, or the grain growth is delayed, the number density of the non-metallic inclusions exceeds 1 000 /cm2. The strain-annealed crystal grain growth ratio becomes less than 2. (Experiment 2) The same result can also be confirmed by the second experiment 2. That is, three flat steel blanks having a thickness of 250 mm formed by the composition shown in Table 1, the residual iron, and the unavoidable inclusions were produced, and the thickness of each flat steel blank was punched by the machining to a thickness of 25 mm, 50 mm, and l. 〇mm and 200mm samples. Thereafter, the samples were heated to 1,070 °C, and after hot rolling to a thickness of 2.5 mm, they were subjected to pickling and cold rolling to a final thickness of 0.5 mm. Next, the conditions of the final annealing annealing (recrystallization annealing) of the continuous annealing type are adjusted to 7 0 0 to 80 ° C to prepare an average recrystallized grain size (in the experimental examples, the examples are simply referred to as average crystal grains). The diameter is 1 2 // m or 14 μm of the product board. The obtained product sheets were subjected to 75 (TC, two-hour strain annealing in an Ar atmosphere. The cross-section of the product sheets (finish-finished annealed sheets) and the strain-sintered sheets perpendicular to the sheet direction was observed by an optical microscope, and The average crystal grain size was measured. Further, the number of densities of the non-metallic inclusions which hindered the grain growth was measured on the product sheet. The results are shown in Table 2, as shown in the table, the grain growth of the product sheet hindered the ductile non-metal. The number of inclusions is -17- (14) 1276693 degrees is less than 100 00 / cm2, and the strain-annealed crystal grains grow relatively large. Table 1 Steel number chemical composition (mass%) C Si Μη 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) 1276693 Table 2 Steel numbered steel slab Thickness (mm) Average crystal grain size strain annealing crystal grain growth ratio hindering grain growth ductility non-metallic inclusion number density (pieces/cm2) Before the strain annealing (//m) After annealing (Qing) 1 25 12 50 4.2 0.3 Inventive Example 50 34 2.8 61 Inventive Example 100 22 1.8 1012 Comparative Example 200 17 1.4 3581 Comparative Example 2 25 46 3.8 0.7 Inventive Example 50 36 3.0 65 Inventive Example 100 26 2.2 811 Inventive Example 200 19 1.6 2778 Comparative Example 3 25 47 3.9 0.3 Inventive Example 50 43 3.6 19 Inventive Example 100 26 2.2 286 Inventive Example 200 22 1.8 1024 Comparative Example 1 25 14 50 3.7 0.3 Inventive Example 50 32 2.4 42 Inventive Example 100 26 2.0 828 Invention Example 200 16 1.2 3731 Comparative Example 2 25 44 3.1 0.5 Inventive Example 50 34 2.4 35 Inventive Example 100 28 2.0 657 Inventive Example 200 22 1.6 2824 Comparative Example 3 25 50 3.6 0.1 Inventive Example 50 43 3.1 11 Inventive Example 100 31 2.2 220 Invention Example 200 23 1.6 1038 Comparative Example -19- (16) 1276693 By limiting the composition as described above and appropriately limiting the number density of ductile non-metallic inclusions that hinder grain growth, the strain-annealed steel sheet can be assembled The average crystal grain size of the core material of the stator contributes to more than twice the particle diameter after the final finish annealing. Thereby, the iron loss of the stator can be greatly reduced. Further, the rotor is used in a state of being finally refined and annealed, and the crystal grain size thereof is relatively small, and high strength, particularly a high upper and lower drop point (hereinafter abbreviated as YP) can be maintained. Further, by using the rotor and the stator described above, it is possible to efficiently assemble a high-performance rotating machine for high-speed rotation. The strength level required for the rotor is different depending on the characteristics of the rotating machine. Therefore, the average crystal grain size of the controlling factor of the strength of the steel sheet is designed to be required for the strength level of the rotor. However, in the case of a general rotary machine, the average crystal grain size of the final finish annealing of the steel sheet is preferably 6 to 2 5 //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. Further, although it is not intended to give an explanation to the scope of the present invention, the reason why the growth ratio of the annealed crystal grains is dominant due to the number density of the non-metallic inclusions which hinder the grain growth is considered as follows. First, it is assumed that the inclusions having the same length as the crystal grain size most hinder the grain growth property. Since the ductile inclusions are present across one or more of the crystal grain boundaries, the probability of hindering the growth of the crystal grains is high. However, when the total amount of non-metallic inclusions present in the electromagnetic steel sheet is -20-(17) 1276693, the volume fraction of the steel may be slightly determined, according to the Zener formula. The possibility that the inclusions which are extremely long in crystal grain size hinder the grain growth property is low. In other words, the extent to which the ductile inclusions impede the grain growth property varies depending on the length of the inclusions. According to the knowledge of the present inventors, the length of the ductile inclusions is 3 to 9 times the average crystal grain size of the final refined annealing sheet. At the time, it is the largest when it blocks the growth of ductile non-metallic inclusions. Therefore, the "strain-annealed crystal grain growth ratio" suffers from the number density of the long-term ductile inclusions, that is, the "straining grain growth ductile non-metallic inclusions", and the so-called Zener formula means suppression. The following formula of the grain growth inhibiting force I of the agent. 1 = (3/4) x(Vxaxp /r〇) where V is the molar volume of the parent phase, cj is the grain boundary energy, p is the volume fraction of the precipitate, and r〇 is the average particle radius of the precipitate.

As described above, the contents of Si, Mn, C, Sol, Α1 and yttrium of the non-oriented electrical steel sheet are respectively controlled, and the number density of the non-metallic inclusions which hinder the grain growth ductility is suppressed to 1 000 / cm 2 . Hereinafter, the strain-annealed crystal grain growth ratio can be increased to form a high magnetic flux density non-oriented electrical steel sheet suitable for a rotary machine. In addition, by limiting the composition of the steel sheet to the content of Ti, Nb and V, or adding Sb, Sn, the effect can be further enhanced. This situation can be confirmed by the following experiment. (Experiment 3) -21 - (18) 1276693

Produce the steel blocks of the composition shown in Table 3, the residual iron and the unavoidable impurities. After heating the steel blocks to 1070 °C, they are hot rolled to 2.5 mm thick, pickled, and then cold rolled to 0. · Final thickness of 5 mm. After further finishing annealing (recrystallization annealing) at 80 ° C for 10 seconds to form a product sheet, strain annealing was performed at 750 ° C for two hours to prepare a strain-annealed sheet. Further, the obtained product sheet and the strain-sintered sheet were punched into the same number of samples parallel to the rolling direction and perpendicular to the rolling direction, and the magnetic flux density and the iron loss were measured in accordance with JIS C 2550. The results of the measurements are shown in Table 3. Further, the average crystal grain size of each of the product sheets was 10 to 20 // m. Further, the number density of the ductile non-metallic inclusions which hinder the grain growth of each of the product sheets is 1000 / cm 2 or less.

-22- (19)1276693 Iron loss (W/kg) After strain annealing 5 00 LO l〇CO CM Seven CM 00 CO Bu CO CD CO Bu CO Bu CO strain annealing before CD CD CNJ CD CO CO in CsJ in T— To CM IT) CO iri CNJ ud CN lO CNJ in % 05 E s 1 IIIII 0.01 I 0.03 ! 0.08 I 1 IIIIII 0.01 0.02 I 0.19 &gt; 0.0010 0.0020 0.0065 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 | 0.0006 o χ- Ο ό [ ! 0.0009 0.0015 0.0004 0.0006 0.0005 0.0004 0.0004 0.0003 〇0.0065 0.0060 0.0065 0.0070 0.0060 0.0055 0.0055 0.0055 0.0060 0.0065 0.0065 2 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 I 0.0001 0.0002 0.0001 0.0001 0.0002 0.0001 0.0001 I 0.0002 0.0001 C 0.15 i 0.17 0.16 0.17 0.18 0.17 0.15 0.17 0.17 0.19 0.15 CO I 0.90 0.90 [ 0.90 0.90 0.90 0.90 0.90 0.90 0.90 0.90 0.90 Ο 0.0018 0,0017 i 0.0025 0.0019 0.0023 0.0021 0.0018 0.0018 0.0022 0.0024 0.0017 疆调τ— CM CO Inch in (D 00 〇&gt; -23- 1276693 Table 4 Steel number chemical composition (mass%) Flat steel blank thickness (mm) C Si Μη Sol.Al N Sb.Sn 21 0.0032 0.75 0.25 0.0003 0.0025 —— 200 22 0.0031 0.80 0.25 0.0004 0.0024 a 200 23 0.0031 0.55 0.26 0.0002 0.0021 a 200 24 0.0032 0.75 0.25 0.0002 0.0017 — 280 25 0.0037 0.80 0.27 0.0003 0.0021 — 280 26 0.0028 0.55 0.25 0.0004 0.0022 a 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 results obtained are shown in Table 5. As shown in Tables 4 and 5, the composition of the composition according to the present invention and the number density of the non-metallic inclusions which hinder the grain growth ductility are relatively large, and the growth of the strain-annealed crystal grains is relatively large, so that the iron loss after strain annealing is particularly low. . In addition to the higher drop point (YP) and Vickers hardness (Hv) of the product (state of final finish annealing), it is also suitable for simultaneous punching to manufacture the rotor and stator of the rotating machine. Of course, the magnetic flux density is also sufficiently high. Further, in the invention examples (27, 29) in which Sb or Sn was particularly added, the magnetic improvement by strain annealing was particularly remarkable. -31 - (28)1276693 Preparation 1 1 Inventive Example Inventive Example Comparative Example Comparative Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Strain Annealing Crystal Grain Growth Ratio 00 CO CO 々in c\i 00 r - σ> τ — CD t— 00 七 CD T- o iri T—Characteristics after strain annealing Β5〇(Τ) i Average crystal grain size (//m) CD CD ID S CO CN σ> 00 m 00 § s W15/50 (W /kg) q inch CO inch CO LO in IT) CD CO LO CO CNJ iri tooth _ a 113⁄4 嫛S good] hit 1 踅 theo ni 讫-蘧m 750 583 955 1525 1072 1998 923 2004 830 1818 product characteristics (strain Before annealing) Vickers hardness one (Hv) 113 "110 115 118 115 114 118 118 G> vx-120 amp 1 298 294 300 295 298 309 309 310 315 311 | average crystal grain size 1 (β m) CM CO 〇gt — CNI CM OJ t— CVJ CNJ B5〇(T) 1 1.75 1.76 1.76 1.73 1.72 1.72 1.75 1.75 1.76 1.74 W15/50 (W/kg) CNI LO iri iri 00 l〇o CD CM CD inch iri t- CD inch LO o CD Steel No. CN CM CO C\J to CM CD CN c\i 00 C\J σ&gt; οι -32- (29) 1276693 (Example 2) Manufactured with the composition of Table VI, the rest A continuous casting flat steel preform with a thickness of 210 mm is formed by the residual iron and the unavoidable impurities. At this time, the slag composition optimization and the hot rolling conditions are appropriately controlled by the steel program to control the amount of non-metallic inclusions which hinder the grain growth ductility. 1 000 pieces/cm2 or less. The obtained flat steel blank was treated in the same manner as in Example 1 to form a product, and was tested in the same manner as in Example 1. However, the final finishing annealing of steel No. 58 was at 680 ° C, The final finish annealing of the steel number was carried out separately at 850 ° C. The results obtained are shown in Table 7. As shown in Table 7, the composition of the composition and the average crystal grain size according to the present invention all have excellent strain annealing crystal grain growth ratio. With strength and magnetic properties, it is suitable for rotors and stators that can be punched and manufactured at the same time. In addition, it is known that the final finishing annealing temperature is controlled at 700 ° C to 8 ° ° C, or the average recrystallization grain size of the product sheet is controlled to 6 to 25 // Μ, for high strength and strain annealing before strain annealing. The effect of both low iron loss is quite favorable. -33- (30) 1276693 Table 6 Steel number chemical composition (mass%) C Si Mil 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 0.001 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 Sn:0.010 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:0.040, 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 0.0004 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 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 0.0050 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 0.0038 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, Sn:0.006, 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: 0.0075 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 0.0001 0.0010 Sn: 0.020 -34- (31) 1276693 Table 7 Characteristics of steel numbered products (should be Before annealing) After strain annealing, the characteristic strain annealing crystal grain growth ratio is prepared W15/5O (W/kg) B5〇(T) Average crystal grain size (β m) Falling point (MPa) Vickers hardness (Hv) W15/50 ( W/kg) average crystal grain 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 Inventive Example 35 5.2 1.74 14 298 103 4.1 48 3.5 Inventive Example 36 5.3 1.75 14 302 104 3.8 55 3.8 Inventive Example 37 5.7 1.76 15 292 103 4.8 48 3.2 Inventive 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 Inventive Example 40 5.1 1.74 14 298 107 3.6 58 4.1 Inventive Example 41 5.1 1.74 13 293 105 3.9 54 4.0 Inventive Example 42 5.2 1.75 14 297 108 3.7 59 4.2 Inventive Example 43 5.3 1.75 15 295 104 3.9 59 3.9 Inventive Example 44 5.5 1.76 15 328 127 3.9 59 3.9 Inventive Example 45 5.8 1.76 16 311 123 4.6 50 3.2 Inventive Example 46 5.8 1.76 14 305 116 4.5 52 3.6 Inventive Example 47 5.9 1.75 13 331 133 4.5 56 4.4 Inventive 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 Inventive Example 54 6.0 1·74 13 308 115 4.9 30 2.3 Inventive Example 55 5.9 1.73 12 311 109 4.8 25 2.1 Inventive Example 56 5.3 1.73 14 297 103 4.2 45 3.2 Inventive Example 57 5.4 1.73 13 295 100 4.5 46 3.5 Inventive Example 58 8.7 1.76 5 341 132 6.2 14 2.8 Inventive Example 59 4.9 1.73 30 272 95 4.4 50 1.7 Inventive Example 60 5.4 1.75 14 330 131 3.7 63 4.5 Inventive Example 61 5.5 1.74 14 315 120 3.9 59 4.2 Inventive Example 62 5.2 1.74 15 295 106 3.7 65 4.3 Inventive Example 63 5.2 1.76 14 304 109 3.8 60 4.3 Inventive Example 64 5.3 1.75 14 305 107 3.9 58 4.1 Inventive Example 65 5.6 1.75 15 301 105 4.0 61 4.1 Inventive Example 66 5.2 1.74 14 297 108 3.7 60 4.3 Inventive Example 67 5.2 1.74 14 298 108 3.6 61 4.4 Inventive Example -35- (32) 1276693 As described above, the invention provides a non-oriented electrical steel sheet which is extremely suitable for the manufacture of a rotor and a stator for a rotating machine. Further, the non-oriented electrical steel sheet according to the present invention is not only such that it has excellent characteristics of so-called recyclability. That is, when the rotating shaft of the motor is cast by a conventional iron core material having a high A1 amount, the surface of the molten iron is oxidized and viscosity-increasing. As a result, the mold filling property of the molten iron is lowered, and sometimes a stable casting cannot be obtained. Therefore, it is generally considered that the scrap iron slag containing A1 lacks recyclability. However, the non-oriented electrical steel sheet according to the present invention is a low A1 material, and the recyclability required for casting is extremely high. INDUSTRIAL APPLICABILITY The high magnetic flux density non-oriented electrical steel sheet according to the present invention is capable of simultaneously taking 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, and imparting rigidity to the stator material. High magnetic flux density and low iron loss. As a result, the manufacturing efficiency and output characteristics of the components for the rotating machine and the rotating machine can be greatly improved. Moreover, the non-oriented electrical steel sheet according to the present invention is superior to the recyclability at the time of casting, and can improve the castability in recycling the scrap iron slag of the punching material. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a graph showing the grain growth ratio of a 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 non-metallic inclusions that hinder grain growth and ductility as a parameter. -36 -

Claims (1)

The members of the grave requested that the case was changed after the amendment was amended. The original application of the patent application No. 92 1 2 1 498 was amended. The amendment of the Chinese patent application dated September 7, 1993 I. A non-directional electrical steel sheet, The characteristics are as follows: When converted by mass percentage, it includes: Si: 0.1% 〜1·2% ; Μη: 0.005% 〇·3%; and C, Al, Ν are respectively limited to: C· 0.0050% or less (including ·); Sol· Α1: 0.0004% or less (including 〇); N: 0.0030% or less (including 〇); the rest is F e and unavoidable impurities, and the average particle diameter D relative to the recrystallized grains is 3 D The number density of inclusions of ~9 D is 1〇〇〇/cm2 or less. 2. The non-oriented electrical steel sheet according to claim 1, further comprising Sb having a mass percentage of 〇〇〇5% to 〇1〇% and Sn having a mass percentage of 0.005% to 0.2%. At least one selected from the combination. 3. The non-oriented electrical steel sheet according to item 1 of the patent application of claim 1 further contains Ni from a mass percentage of 〇〇〇丨% to 〇2% and a mass percentage of 0.001% to 〇·2% of Ni. At least one selected from the combination formed. 4 · If you apply for a patent scope! Non-directional electrical steel sheet Further, 1276693 further contains at least one selected from the group consisting of a mass percentage of 〇·〇〇〇ι% to 0.10% and a mass percentage of 0.0001% to 0.01% of Ca. 5. In the above-mentioned unavoidable impurities in the non-oriented electrical steel sheet of claim 1, the content of Ti, Nb and V is determined to be 0.0020% or less (including 0) of Ti; Nb is 0.0050% (including 〇) ); V is 0.0060% or less (including 0). 6. In the above-mentioned unavoidable impurities in the non-oriented electrical steel sheet of claim 1 of the patent application, the mass percentage of S and 0 is 0.0050% or less (including 0) in S; Ο is 0.0100% (including 〇) . 7. The average grain size D of the above recrystallized grains in the non-oriented electrical steel sheet of claim 1 is 6 // m to 2 5 // m. 8. The non-oriented electrical steel sheet according to claim 1, wherein the steel sheet is a steel sheet produced by at least cold rolling and subsequent final annealing annealing, and the temperature of the final finish annealing is 700 ° C -t. 9 • The non-oriented electrical steel sheet of claim 1 is subjected to strain annealing at 750 ° C for two hours to increase the average particle size of the crystal grains by more than two times. A non-oriented electrical steel sheet, which is produced by applying a fire to a steel sheet according to any one of claims 1 to 9. 11 · If the non-directional electromagnetic steel REM is in the scope of patent application No. 10, it is limited to the following, and it is limited to the following, and its process is ^ 800, which may be re-released as a declaration, -2- 1276693 wherein the temperature of the strain annealing is 700 ° C to 800 ° C. A rotor member for a rotary machine, characterized in that the rotor member for a rotating machine is obtained by stacking the non-oriented electric steel sheets according to any one of the first to ninth aspects of the patent application. 1 3 . A stator member for a rotating machine, characterized in that: The stator member is formed by stacking the non-oriented electrical steel sheets according to any one of the first to ninth aspects of the patent application, and then performing strain annealing. A rotary machine, comprising: the rotor member for a rotating machine according to claim 12; and the stator member for a rotating machine according to claim 13 of the patent, wherein the rotary machine Both the rotor member and the stator member for the rotating machine use the same non-oriented electrical steel sheet as a material.