TWI312371B - - Google Patents

Description

1312371 · IX. DESCRIPTION OF THE INVENTION: TECHNICAL FIELD The present invention relates to a high-strength non-oriented electrical steel sheet and a method of manufacturing the same. The steel plate of the present invention is particularly exemplified by a rotor of a high-speed rotating machine. Suitable for electromagnetic parts that are subject to large stresses. Here, the "high-speed rotating machine" may be, for example, a turbine generator, an electric vehicle, a hybrid motor drive motor, or a robot or a machine tool. [Prior Art] In recent years, the frequency control of the drive power source can be controlled by the progress of the drive system of the motor. Therefore, the variable speed motor and the motor that rotates at a high speed above the commercial frequency are increasing. In the motor rotating at such a high speed, the centrifugal force ' acting on the rotating body' is proportional to the radius of rotation and increases in proportion to the second power of the rotational speed. Therefore, rotor materials, especially for medium and large high speed motors, must have a south strength (especially a tensile strength). Further, in recent years, an inverter-controlled brushless DC motor has been increasingly used in drive motors and compressor motors of hybrid automobiles, and a gap is provided in the rotor. (slit) embed a magnet. Therefore, in the rotation of the motor, the stress concentrates on the narrow bridge between the slits, so the core material used for the rotor must have high mechanical strength. In addition, since the stress state changes with the acceleration of the motor, the 312XP/invention manual (supplement)/96-03/95147048 5 1312371 changes with vibration, so the heart used by the rotor (iron core) has high fatigue strength. It is better. On the other hand, since the rotating machine such as a motor and a generator uses electromagnetic phenomena, the mandrel must have excellent electromagnetic properties (also electrop, low iron loss (ir〇n loss), It is better to have a high magnetic flux density (magnetic flus density). In particular, in the high-speed rotating motor, since the eddy current generated by the high frequency causes the motor efficiency to decrease, the high-frequency _ iron loss is low (that is, the high-frequency iron loss characteristic is excellent). Usually, the rotor mandrel is used as a layered layer of a non-oriented electrical steel sheet which is punched. However, in the case of a high-speed rotary motor, the material of the rotor does not satisfy the above mechanical strength, and a higher-strength cast steel rotor must be used. However, since the rotor made by the pray is not a laminate, the eddy current loss is much higher than that of the rotor laminated with the electromagnetic steel sheet. Therefore, an electromagnetic steel sheet having excellent magnetic properties and high strength has been expected as a material for a rotor. For the method of increasing the strength of the steel sheet, there are known solid solution hardening, precipitation hardening, fine-grain hardening, and complex-phase hardening. 'Wei' these strengthening methods all cause deterioration of magnetic properties, so it is often extremely difficult to balance strength and magnetic properties. Under this condition, there have been several 312XP/invention manuals (supplements)/96-03/95147048 6 1312371 on high-strength non-oriented electrical steel sheets. For example, it is proposed in Japanese Laid-Open Patent Publication No. Sho 60-238421 that the content of Si in the southern part is 3.5 to 7 % (% by mass, the same applies hereinafter), and further, Ti added for solid solution strengthening, w, Mo, Mn, Ni, c〇, Ai_, -: method of high strength. In addition, in the 特 专利 专利 专利 么 么 么 么 么 么 么 么 么 么 么 么 么 么 么 么 么 么 么 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 5 The method of the feature. > Using raw material from the raw material of the New Zealand factory, drying the valley after hot rolling, causing problems such as plate breakage, resulting in a decrease in yield or a shutdown

The 'related plate breakage' can change the cold milk system to a plate temperature of several hundred. C

Uing) to alleviate. However, in order to carry out the warm-drying system, j has the corresponding equipment, and the production is subject to the burden of process management. Such as the spear level plus ^ i various # proposers are: in the Japanese patent special Kaiping 2-such as 42 Gongqiang: two rsi content 2. ° ~ 3 · 5% of the steel ... 嶋 solid solution 6 ~ 330255 ζ τ · 3 〇 〇 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 4.0 The solution strengthening is expected to take care of both. However, the Japanese Patent Unexamined No. 2-22442 cannot be used to obtain sufficient strength. This patent is used to open the patent. 6 = ^^ 312XP/g_^(supplement)/96·03/95147048 7 1312371 The method of the Japanese Patent Publication No. 2-8346 discloses that the magnetic characteristics are greatly reduced when high strength is obtained, and there are technical problems. Further, the fatigue properties of the steel sheet produced by the above method were evaluated. As a result, it was found that the desired fatigue strength could not be obtained when high strength was obtained. That is to say, most of them are those which can improve the yield strength and the tensile strength of the steel but fail to improve the fatigue characteristics. Therefore, the material design method considering the fatigue characteristics in the present situation has yet to be established. Regarding the high-strength electromagnetic steel sheet which is focused on the fatigue property, it is proposed in Japanese Patent Laid-Open No. Hei. No. 234 303, that the crystal grain size is controlled by the composition of the electromagnetic steel sheet having a content of 3 or less. The technique of fatigue limit above MPa. However, with this method, the level of fatigue limit reached is still low (up to about 430 MPa in actual performance), but it cannot meet the level required recently. For example, the fatigue limit (such as coffee limit): 500 MPa or more. Regarding the method of manufacturing a high-strength electromagnetic steel sheet, there have been other proposals. In Japanese Patent Laid-Open Publication No. Hei 2--113185, it is proposed that a steel containing 0.2 to 3.5% Si is left to be processed inside the steel. Work hardening structure, in order to achieve high-strength technology. The specific method disclosed is that it is not subjected to heat treatment after cold rolling, or even if heat treatment is performed, it is not required to be maintained at a level corresponding to 75 〇t or more for 3 sec seconds or more, preferably at 7 〇〇. <t or less, especially t: below, 6〇〇. (: The following, 55 (TC below is better. In addition, the exemplified performance is 'the processing organization rate under 750 ° C-30 seconds annealing (10), 20% in °C-30 seconds, at 600 ° C -30 seconds is 5〇%. 312XP/Invention Manual (Supplement)/96-03/95147048 1312371 In this case, since the annealing temperature is low, the shape of the helmet is corrected, which is a problem. 10. The stacking rate after the motor is used as a mandrel, etc.

Ua_tlon factor) will be reduced, and the distribution of the stress will be uneven, etc., all of which are problems. The final annealing of the 'normal' non-oriented electrical steel sheet is carried out in a continuous annealing furnace. In order to suppress oxidation of the surface of the steel sheet in the furnace, it is usually adjusted to an atmosphere of hydrogen gas having a percentage or more. In such a continuous annealing apparatus, in order to perform low-temperature annealing of less than 7 GGt, the switching of the furnace temperature setting takes time and in order to avoid hydrogen explosion, the atmosphere in the furnace must be replaced, which imposes a cautious restriction on the operation. , " Furthermore, in the case of high-temperature final annealing or coating coating_baking treatment, etc. (such as Shikou, by re-rolling into the processing organization), the process must increase 'causes cost Increased and limited on the device. Further, the insulating coating on the surface of the steel sheet which is applied and baked after the final annealing is destroyed by the subsequent treatment, resulting in a problem that the insulation is lowered. In the composition of Si: 4.0 to 7.0%, the steel sheet after cold rolling is specified by a specific temperature specified in relation to the Si content. The heat treatment is carried out to make the recrystallization rate of the crystal structure 95% or less, and the rest is essentially a work-oriented structure, in order to achieve the purpose of strengthening the purpose. In this formula, for example, when the heat treatment is performed at 700 ° C, it is necessary to use about 9% or more of Si to obtain a high tensile strength of 80 kgf/mm 2 or more, a degree of stretchability, and excellent A practical soft magnetic material with magnetic properties. 312XP/Inventive Manual (Supplement)/96-03/95147048 9 1312371 Further, it is proposed in Japanese Patent Laid-Open Publication No. 2005-264315 that: in the case of containing Si: 0·2~4 shoulders, ferrite is used. In the phase-oriented electromagnetic steel sheet, 'addition of Ti, sen, Ni is equal to the internal diameter of the steel 〇〇5〇

An intermetallic compound below Am for the purpose of achieving the purpose of strengthening. According to this technique, a non-oriented electromagnetic steel sheet having a tensile strength and wear resistance of 6 Gkgf/? or more and excellent magnetic flux density and iron loss can be produced without impairing cold rolling properties. SUMMARY OF THE INVENTION (Problems to be Solved by the Invention) Generally, there has been a large number of non-directional magnetic steel sheets for two strengths. In order to ensure the necessary strength and good 峨: 'The failure to use ordinary electromagnetic steel sheets The equipment is manufactured in an industrial context. The above is based on the general non-directional electrical steel sheet = the shape of the steel sheet and the magnetic properties are excellent, and the manufacturing method thereof. Further, another object of the present invention is to provide a high-strength and fatigue property, and a manufacturability - a magnetic material having a different magnetic property, an advantageous manufacturing method thereof, a non-oriented electrical steel sheet, and a means for solving the problem. Description: A non-directional electrical steel sheet characterized in that the composition of the forming tool is %.C and N:C in mass %. 010% 312XP/invention specification (supplement)/96-03/95_8 10 1312371 The following and N are below 0. 010%, and are suppressed to C+N$0. 010%; Si: 1. 5% or more and 5. 0% or less; Μη: 3. 0% or less; A1: 3. 0% or less ; P : 0. 2% or less; S : 0. 01 % or less; further containing Ti: 0. 05% or more and 0·8% - below, and satisfying the range of Ti / (C + N) 2 16; The part is Fe and the unavoidable impurities; and the ratio of the non-recrystal 1 ized (recovery structure) in the steel sheet is 50% or more. Here, the recrystallization and the non-recrystallization of the recovery structure are explained. First, "recrystallization" is a phenomenon in which a crystal grain having a low defect density and thermodynamic stability is formed, and a matrix having a high defect density (matr iX) is grown while growing. In the recrystallization, the fineness of the crystal grain boundary is sharply reduced. On the other hand, the term "recovery" refers to the phenomenon that the deformation energy is lowered by the passage of the grain boundary, but the defect itself is thermally reduced and the displacement density is lowered. The recovery is clearly observed under the conditions of an annealing temperature of 500 ° C or higher under continuous annealing for a short period of time, which is usually used for non-oriented electrical steel sheets. The recovery tissue and the recrystallized structure can be mixed, and at the higher temperature annealing, recrystallization is more advantageous. In the electromagnetic steel sheet of the usual composition, recrystallization is performed violently at 60 to 65 ° C or higher, and at 700 ° C or higher, most of them become recrystallized structures. Further, in the steel annealed at 500 ° C or higher, the recrystallized structure and the recrystallized recovery structure can be easily distinguished by observation using a tissue (microscopic structure: microstructure) of an optical microscope. Here, the tissue observation can be carried out by using the Natal 312XP/invention specification (supplement)/96-03/95147048 11 1312371 (nital) (by nital nitrate solution: usually used in the direction of the thickness of the plate. A nitric alcohol solution or the like is used for the remainder. Further, in the invention of the above (1), it is preferable that Si: L 5% or more and 4 % (% (all of which are the mass%). Further, in the invention of the above (1), it is preferable to further contain, in mass%, selected from the group consisting of Ni: 〇. Bu 50%, sb: 〇· 002~0. 1%, Sn: 〇. 〇〇2~〇. 1%, b: 〇. 〇〇卜0·01%, Ca: 〇. 001 ～0. 01%, Rem: 〇. 〇〇卜〇. 〇1% and c〇: 〇· At least one of the groups consisting of 2 to 5 %. These preferred conditions can also be freely combined. (2) - A method for producing a non-oriented electrical steel sheet of a strength, characterized in that a steel sheet having the following composition is hot-rolled; and then cold-rolled steel is produced by cold-rolling or warm rolling to obtain a final sheet thickness The anneal temperature is 70 (rc or more, 85 or less, and the strip unit tension in furnace is 2. 5 MPa or more and 20 MPa or less; The component composition is, in terms of mass%, contains: C and N: C is 0. 〇1〇% or less and n is 〇. 〇1〇% or less, and suppression _ at C+NS0. 010%; Si: 1. 5 % or more and 5.0% or less; Μη: 3. 0% or less; Α1: 3. 0% or less; ρ: 〇·2 mass. /. below; s: 〇〇1% by mass or less; further containing Ti: 〇 〇 5 mass % or more and 〇 8 mass % or less, and to satisfy the range of Ti / (C + N) 216. Here, the furnace tension is the inner furnace section of the steel strip at the highest temperature in the annealing furnace The tension per unit area of the steel strip (mostly the heating section or the soaking section). Further, in the invention of the above (2), preferably In the same manner as the above (丨) invention, the remainder of the composition of the slab is Fe and the impurities of the inevitable 312XP/invention specification (supplement)/96-03/95147048 12 1312371. pm is as described above (2) In the invention, it is preferable that the invention (1) = ground' contains, by mass%, Si: 1m4 (10) or less, and/or further contains, by mass%, selected from w: 〇.〇〇2~ O.1%, Sn: 〇〇〇2~〇1%, B: 〇〇〇i~〇._, Ca: =01~〇· GU, Rem: G. Xie~G.(10) and Cg: G. (2) The invention of the above (2) is particularly suitable for producing the steel sheet of the invention of the above (1), that is, the ratio of the presence of the non-recrystallized recovery structure is an area ratio. In the case of the above-mentioned problem, the inventors of the present invention have intensively studied the influence of the various methods of the non-oriented electrical steel sheet on the manufacturability, mechanical properties, fatigue properties and magnetic properties of the non-oriented electrical steel sheet. The manufacturability of the alloy composition for the high-δ gold-magnetized steel sheet (increased the addition amount of the Si (tetra)-solubilizing strengthening element for m-density strengthening) In other words, the effects of the bending characteristics and cold rolling properties of the hot rolled sheet and the hot rolled annealed sheet are discussed in detail. As a result, the carbonitride forming elements have the following findings: (a) by The solid solution c and N are reduced as much as possible, and even in the alloyed steel containing Si of more than 35 mass/〇, the rolling property can be greatly improved. (b) For this reason, it is effective to reduce the amount of C and N while adding a carbonitride-forming element such as Ti, V, Nb or Zr having a sufficient excess amount of c and n. Based on the above findings, in the manufacture of high-alloy electromagnetic steel sheets, the problems in the process such as plate fracture can be greatly reduced, and high productivity can be achieved. Tian / - 312XP / Invention Manual (Supplement) /96-03/95147048 13 1312371 Secondly, the influence of these carbonitride forming elements on the electrical, fatigue and magnetic properties of the electromagnetic steel sheet is also investigated and High tensile strength is effective, and on the other hand, it will cause fatigue characteristics and magnetic properties (iron loss and magnetic flux density) to deteriorate. Right W) In contrast, Ti, v, N=, and z which are excessively added to c and N have a solid solution strengthening effect, which not only improves the tensile strength but also improves the fatigue characteristics = and the deterioration of the magnetic properties is compared with the case of precipitation strengthening. Can be greatly reduced. Furthermore, as a result of examining the effects of the main solid solution elements on mechanical miscellaneous, fatigue, and magnetic properties, the following findings were found: • (e) Among the main elements added to the non-oriented electrical steel sheet,

The solid solution strengthening of Si is considered to be the most effective in terms of both mechanical properties and magnetic properties. However, if the amount of Si added is excessive, the tensile strength (tensile resistance) is increased, and the fatigue characteristics are largely deteriorated. That is, in order to uniformly improve the mechanical characteristics and magnetic properties of the machine, the amount of Si added must be within the optimum range. φ The present invention has been developed based on the above findings, and the gist of the invention is as follows: (3) (3-1) A high-strength non-oriented electrical steel sheet excellent in manufacturability and excellent in fatigue characteristics and magnetic properties. It is characterized in that the composition thereof is contained in mass%: C and N: C is 〇.010% or less and N is 〇〇1〇% or less and 疋 is C+NS 0. 010%, Si: 3. 5% or more and 5.0% or less, Μη: 3. 0% or less, Α1: 3. 0% or less, Ρ: 〇·2% or less, and s: 〇. 〇1% or less, and each has Ni. 5.0% In the following, one or two of Ti and v are contained, and 312Xp/invention specification (supplement)/96-03/95147048 14 1312371 is 0.01% or more and 0.8% or less in total, and satisfies (Ti+v). The range of /(c+N) is the Fe and the inevitable impurities. (3-2) A highly non-oriented electrical steel sheet excellent in manufacturability and excellent in fatigue characteristics and magnetic properties, characterized in that the component composition is such that, in terms of Berry, C and N: C are 〇· 010% or less and N is 〇. 〇1〇% or less and is defined as C+NSO· 010%, Si: 3. 5% or more and 5.5% or less, Μη: 3. 0〇/〇 or less, Α1: 3.0% In the following, Ρ: 2% or less, and s: 〇.〇1% or less, and Ni. 5·0% or less, and one or two of Nb and Zr are contained, and the total is 0.01 G/ ◦ is 0.5% or less, and is in the range of (Nb+Zr)/(c+N)^10, and the rest is Fe and unavoidable impurities. (3-3) A high-strength non-oriented electrical steel sheet excellent in manufacturability and excellent in fatigue characteristics and magnetic properties, characterized in that it contains, by mass%, c and N: C are 0.010% or less and N is 〇 〇1〇% or less and set to C+Ng 〇. 010%, Si: 3. 5% or more 5. 0% or less, Μη: 3. 0% or less, A1: 3.0% or less, ρ: 0.2% or less, And s: 0.01% or less, and contains: 5. 0% or less, and contains at least one of Ti and V, and at least one of Nt> and Zr, which satisfies 〇.〇l%g (Ti+v +Nb+Zr)g〇.5%&(Ti+V+Nb+Zr)/(C+N)2 16 range, the remainder being Fe and unavoidable impurities. (3-4) The high-strength non-oriented electrical steel sheet which is excellent in manufacturability and excellent in fatigue characteristics and magnetic properties, according to any one of the above (3-1) to (3-3), further containing a selected one from below 1 or 2 or more of the groups formed as described above; Sb of mass %: 0. 002~0.1%, Sn: 0. 〇〇2~〇. 1%, B: 〇〇1 〇1% ,

Ca: 0. 001 〜0. 01%, Rem : 0. 00 Bu 0· 01% and c〇 : 〇. 2~5. 0%. 312XP/Invention Manual (Supplement)/96-03/95147048 15 1312371 (4) A method for producing a high-strength non-oriented electrical steel sheet excellent in manufacturability and excellent in fatigue characteristics and magnetic properties, characterized in that 3-1) The composition shown in any one of the inventions of the above-mentioned (3-4) is hot-rolled after the steel chain is formed, and after performing hot-rolled sheet annealing as needed, by performing cold rolling or warm rolling Alternatively, cold rolling or warm rolling of secondary annealing or more may be added to form a final thickness, and then annealing is performed under the conditions of an annealing temperature of 700 ° C or more and 1050 ° C or less. The first plate thickness is preferably set to 0.15 inches or more. • According to the present invention, in particular, the inventions of (1) and (2) above, by standardizing composition and organization, can provide high strength and shape of the board without increasing the limitations of the steel sheet manufacturing and additional steps. A non-oriented electrical steel sheet excellent in magnetic properties. Further, according to the invention, in particular, the inventions of (3) ((3-1) to (3-4)) and (4) can be stably obtained not only with high strength, excellent magnetic properties, but also excellent fatigue properties, and A non-oriented electrical steel sheet excellent in manufacturability. [Embodiment] * Hereinafter, "%" of the relevant components is % by mass unless otherwise stated. [Principle of the Invention] First, the principle of the inventions of the above (1) and (2) will be described. The inventors of the present invention have intensively studied the hand of a non-oriented electrical steel sheet which is industrially stable and has a good shape and which has both high strength and magnetic properties. The high strength required here is specifically 600 MPa or more, more preferably 700 MPa or more, and particularly preferably 800 MPa or more. Further, the required magnetic characteristics, especially the high-frequency low-iron loss characteristics, 312XP/invention specification (supplement)/96-03/95147048 16 1312371, for example, a plate thickness of 3535mm 50W/kg or less is preferable.

The non-directional electromagnetic surface rW, the Wl 〇 / _ value in the plate is 40W / kg or less for the sake of "fishing better, especially 3 〇 w / kg 夕, ° fruit found. Especially the tensile strength exceeds 700MPa The two strengths (4) are effective in suppressing recrystallization and maintaining the recovery structure in the final annealing of the steel sheet structure. (9) The non-oriented electromagnetic steel sheet of the steel composition is required to obtain a recovery structure, and the final annealing temperature is necessary. T is finally annealed at a low temperature below C. For such low-temperature annealing, it is necessary to solve the problem of deterioration of the steel sheet, substitution of the annealing environment gas, change of the furnace temperature condition, and work load. Therefore, under various investigations on the steel composition, it was found that by adding Ti to the c and N in excess, the steel composition can be stably obtained even at a final annealing temperature of 7 〇〇 or more. The annealing of a normal non-oriented electrical steel sheet is equivalent to a high-strength recovery structure (Experiment 1), that is, in Figure 1, the amount of Ti added and the final annealing temperature (soaking time 20/sec) are subtracted. Low is c + β 〇 · 〇 1% of 2. 8% Si_〇. Following i steel: =,, '. The result of the influence of aa behavior. Here, the abscissa in the curve is (quality: M: /〇 座; ^ is the annealing temperature (°c), the number in each circle is the recrystallization rate (recrystallizati (10) ratio) (;%) under the condition of Erhai, and, again, the recrystallization rate is by the plate The optical structure observation result in the thick direction section was obtained, and the ratio of the recrystallized recovery structure was determined (the area illusion was 1 〇〇 _ re-crust rate (area %). ° 曰 312XP / invention manual (supplement) / 96-03 /95147048 17 1312371 In general, in the non-oriented electrical steel sheet, Ti is a harmful element that deteriorates magnetic properties, and is usually suppressed to 0.005 mass% or less. Since the Ti _ content is high, it is urgency at 650 ° C or higher. Recrystallization is carried out, so that it is necessary to stabilize the ground to obtain a recovery structure, and it is necessary to perform final annealing at a low temperature of 600 ° C or less. - On the other hand, we have found that if more than 0.05% by mass of Ti is added, the recrystallization starting temperature will be Since it rises by 100 ° C or more, it can be stably obtained even at an annealing temperature of 700 ° C or higher which has been industrially performed. Therefore, by setting the final annealing temperature to 700 ° C or more and 850 ° C • or less, the furnace internal tension is 2. 5 MPa or more and 20 MPa or less, and the recovery structure can be stably obtained, and the shape of the steel sheet can be favorably controlled. The high-strength non-oriented electrical steel sheet excellent in high strength, magnetic properties, plate shape, and productivity is produced in 焉. Next, the principle of the inventions (3) and (4) above will be described. The experimental results which are the basis of the present invention are explained. (Experiment 2) First, in order to investigate the influence of the steel composition on the manufacturability of the high alloy steel® having a Si content exceeding 3.5%, it is possible to manufacture ultra high purity steel. In the vacuum high-frequency melting furnace, the amount of Si is controlled in a range of 4.:1 to 4.3%, and the test steel blocks having various changes in C and N amounts are melted. 5毫米。 Then, the obtained steel block was hot rolled to a thickness of 2 匪, and then annealed at 900 ° C, and then cold rolled to a thickness of 0. 35mm. At this time, the hot rolled annealed sheet was cut into a 3Oirnn width, and a reverse bending test was performed at a temperature of 30 ° C with a bending radius of 15 mm and a bending angle of 90° to enter the 312XP/invention specification (supplement)/96-03/ 95147048 18 1312371 ^ Simulated evaluation of the passability of steel plates on the manufacturing line. Further, in this case, it is known that the bending condition of the 'and the human' is repeated, and it is known that the edge crack depth (edge crack leng1; h) of the end face of the hot-rolled annealed sheet is cold as the damage frequency increases on the manufacturing line. Evaluation of rolling properties. The results are shown in Figures 2A and 5D. Here, the transverse coordinate of the curve is fC+N)i (mass%) in the steel, and the ordinate is the steel plate passability (the number of bends) and the cold rolling property (the edge crack depth of the end face of the rolled plate) of the manufacturing line. (mm). 2, as shown in Fig. 3, it is known that the steel sheet passability (bending characteristics of the hot rolled sheet) and the cold rolling property (edge crack depth) of the manufacturing line, that is, the manufacturability phase are locally dependent on the total of C and N; In other words, if the total of (10) is reduced to 0.0015% or less, the alloy steel having a high yield of 4 strokes is sufficiently manufacturable, and if the amount of C + N is increased, the manufacturability is rapidly deteriorated. : The current technology of using general equipment such as converter refining and degassing secondary refining + it is extremely difficult to maintain the C+N amount 〇 〇 1(10) or less. (Experiment 3) Therefore, in consideration of whether or not the solid solution c and N in the steel are the main cause of the decrease in the manufacturability of the evaluation, it is necessary to add a carbonitride-forming element to attempt to precipitate and fix C and N. That is, the amount of Si is suppressed in the range of 4_b.4.3% in an electric furnace, and the total amount of C+N is controlled in the range of (丨)〇〇〇38~〇〇〇48%, (magic The range of 0.0074~0.0092%, (3) 〇.0175~〇〇196% range, (4) 0· 0353~0. 0391% of the range of 4 levels, and then the Ti addition amount 312XP / invention manual (complement ()) /96-03/95147048 19 1312371 made various changes to make steel blocks. Then, after hot rolling to further hot-rolled sheet annealing, cold milk to the board with '0.35mm, then 950t The final annealing is carried out. von/the sample thus obtained is examined in the same manner as described above, and the steel sheet passability (bending property of the hot-rolled sheet) and the depth of the cold-milk edge crack of the clothing line are examined in the same manner as described above. The results are shown in Figure 7. The abscissas of Figures 4 and 6 are the amount of Ti in the steel (% by mass), and the abscissas of Figures 5 and 7 are the ratio of (10) (the ratio of the amount of steel te to the amount of N in the steel (% by mass), That is, 纵ι/((10). Again, Fig. 4 and Fig. 5) ordinates are the plate passability (f-number of times) of the manufacturing line, and the ordinates of Fig. 6 and Fig. 7 are cold-drying Wei j柹r I ( The depth of the crack on the edge of the rolling plate is (ram). In addition, the figure shows that "^ ^ Τ", the manned shape "♦" indicates the above-mentioned level of C + N '2, the color square "_" The above level (2) is indicated, the black triangle "▲" indicates the level (3), and the "x" symbol indicates the above level (4). From this result, it can be seen that by adding about 4 times the atomic ratio of C + N: 5 (: 1: The amount is 16 times or more) Ti is excessively added, and the hot rolled sheet can be greatly improved, even at a C+N amount which is industrially capable of a large amount of purity. It is also possible to manufacture high-alloy steels in a stable manner. However, if C+N is too much in summer, the manufacturing improvement effect due to the addition of L is improved, and the number of times of writing and the depth of cold-rolled edge cracks are all industrially Level of problem (F-number of times: less than 1 () times, edge degree: more than 3 mn 〇.: The ash can sufficiently improve manufacturability even if it is added by Ti. The intermediate "Tl addition I may deteriorate if it exceeds manufacturability. Furthermore, 312XP/Invention Manual (supplement)/96-〇3/95147〇48 20 1312371 :ΓN=二添:? Less: the composition of the 'and T i added excessive amount—breaking; 2 when dry The edge crack depth is more than 10 sides, and _ (Experiment 4) test, '2 to the steel plate is cut in parallel with the milk direction to test the fatigue characteristics. Here, the mechanical properties, the tensile strength in the evaluation. In addition, the fatigue characteristics are based on the fatigue test piece of Ping Er Pan ^, and the stress ratio: Qi, solution: the partial tensile (stretch-stretch) fatigue test of z is investigated, and 10 million (107) is obtained. After the cycle, the maximum stress of the plate fracture did not occur as the fatigue ultimate strength. The knot obtained is shown in Fig. 8 and Fig. 9. Here, the abscissa of the curve is the steel in the steel (% by mass), Fig. 8 The vertical coordinate is the tensile strength (Ts) (Mpa), and the vertical coordinate of Figure 9 is the fatigue limit (MPa). In addition, the mark of the point and the amount of C + N Lu The horizontal relationship is the same as that of Figs. 4 to 7. As shown in Fig. 8, the tensile strength TS increases as the amount of Ti increases, and the effect becomes more remarkable as the amount of C+N increases. +N is more steel in the south, which is strengthened by precipitation precipitation due to the precipitation of carbonitrides of τ i; on the other hand, the amount of steel and Ti added with a low C + N amount is sufficient for the amount of C + N The excess steel is mainly due to the high strength due to solid solution. Also, as shown in Fig. 9, the fatigue limit is the opposite of the tensile strength when compared with the same Ti addition level. The group with a low C+N amount shows the :: characteristic of the 312XP/invention specification (supplement)/96-03/95147048 21 1312371. The reason for this is that it is considered that the amount of C+ Ν is high and the carbonitride is likely to be formed to be large, and the amount is large, which is a cause of fatigue damage. The measurement was performed by cutting the same number of magnets in the direction perpendicular to the rolling direction of the rolling and the results of the magnetic properties evaluation by the Epstein method, Fig. 10. Here, the horizontal coordinate of the curve is Ti ^ high frequency talk one kg in steel, and the mark of c + N level is the same as Figure 4~9.

As shown in the figure, the group with a high C+N amount adds a small amount of η day: 'The iron loss characteristic deteriorates violently. In contrast, (10) the amount of the suppressed group is due to the addition of Ti. The iron loss is slightly deteriorated. From the results of the above investigation, it can be known that in order to obtain a non-oriented electrical steel sheet which can satisfactorily satisfy the industrially satisfactory manufacturing property and the opposite requirement of fatigue characteristics, the amount of C+N must be reduced as much as possible in the industry. In the case of high-alloy steel, it is important to use Ti as an element for preliminarily fixing C and N which are solid-solved and as a solid solution strengthening element. According to the above findings, an appropriate amount of carbonitride forming element (v, rib, etc.) such as Ti is appropriately added to the high alloy steel in which the amount of C+N is reduced as much as possible in the industry.

Zr) 'based on this steel' systematically evaluates the effects of alloying elements such as μ, Mn, μ, w, and p to clarify the optimum steel composition conditions. [Steel composition] Hereinafter, the reason for limiting the component composition range of the present invention based on the above findings will be described. 312XP/Invention Manual (supplement)/96-03/95147048 22 1312371 This c: 〇·〇1〇〇/0 or less and N: 0.010% or less, and c+Nso.oio% In the present invention, C and N are In the solid solution state, there is a harmful element that significantly reduces the manufacturability of steel, but it is formed by adding Ti or an appropriate amount of carbonitrides such as Nb, V, and Zr (described in (3) (4)). Elements can reduce the negative impact on manufacturing and the level of unobstructed production on industrial scale. However, the formation of carbonitrides causes deterioration of magnetic properties and even fatigue characteristics, so that C and N are preferably minimized. Therefore, it is preferable that 匸: more preferably, C: 0.0005% or less and N: 0.0005% or less, and particularly preferred, C: 0.003% or less, and N: 0.003%. 〇 and w are not necessary, but the lower limit that can be lowered in industry is 〇 〇〇〇 1%. Wood Si: 1. 5% or more and 5. 0% or less:

In addition to being used as a deoxidizing agent, Si also has an effect of increasing the electrical resistance of steel and reducing iron loss, and is a main element constituting a non-oriented electrical steel sheet. And has high solid solution strengthening energy. In other words, compared with other solid solution strengthening elements such as Mn, Al & Ni added to the non-oriented electrical steel sheet, it is the most balanced element for high tensile strength, high fatigue strength and low iron loss. 5%以上。 Adding 1.5% or more in the present invention (1), (2). More than 2. 〇% or more. More than 35% of the present invention (3) and (4) are more actively added, and the application of the increase in the amount of Si increases the tensile strength, the fatigue ultimate strength, and the iron loss to achieve high characteristics. On the other hand, when the amount of Si exceeds 5.0%, the tensile strength increases, however, the fatigue ultimate strength is rapidly lowered, and cracking occurs in the cold milk production to reduce the manufacturability. The reason for this is that we believe that the 312Χί>/invention specification (supplement)/96-03/95147048 23 1312371 rule is generated due to the high level of production. Further, if the amount of Si exceeds 3.0%, the toughness starts to decrease, and if it exceeds 4.0%, the toughness deterioration is clearly manifested. In addition, when it exceeds 0.5%, the deterioration of toughness becomes remarkable, and the control of the higher degree of the steel sheet during the passage and rolling of the steel sheet causes a decrease in productivity. Therefore, above S i is limited to 5·〇%. It is preferably set to 4.0% or less. In the case of the inventions (1) and (2), it is preferable to set the stress to be 3.5% or less. *Ti : 0.05% or more and 0.8% or less, and Ti/(C+N)^16 (Invention (1), (2)) • * Any of the following conditions (Invention (3), (4)) (3 -l) Ti+V : 〇. The above 〇. 8% or less, and (Ti+v)/(c+N)g 16, —(3-2)Nb+Zr: 0.01% or more and 0·5% or less, And (Nb+Zr)/(c+N) 2 10, or (3-3)0. (Ti+y+Nb+Zr)S 〇. 5%, and (Ti+V+Nb+Zr) /( C+N)^16 Τι is an important element in the invention. In other words, Ti has an effect of increasing the recrystallization temperature of the steel, and has a state in which the final annealing temperature of the steel sheet is increased to 750 C or more, and the unrecrystallized structure remains sufficiently in the inventions (1) and (2). . Further, Ti can be used as a solid solution strengthening element to benefit the tension. In order for these effects to be exerted stably, it is necessary to be Ti: 0.05% or more and Ti/(c+N)^l6. On the other hand, if Ti exceeds 0.8%, it is liable to cause a defect called "spot", resulting in a decrease in manufacturability and yield, so it is limited to 8%. In addition, Ti forms carbonitrides, and solid solution C and N precipitated in steel 312XP / invention manual (supplement) / 96 · 〇 3 / 95147 〇 48 24 1312371 fixed 'has improved manufacturing of high alloy steel The effect of sex. Further, it can function as a solid solution strengthening element, which is effective for high tensile strength and high fatigue strength. In particular, in the case where Si is added in an amount of more than 3.5%, the solid solution strengthening is utilized in the most extensive inventions (3) and (4), and these effects are fully utilized. That is, the content is determined such that V of the same carbonitride-forming element-solid solution strengthening element is 〇. 0U or more 〇. 8% or less ' and (Τί+ν)/(α+Ν)^ a. In order for C and 开始 to be settled and fixed in the middle of the manufacturing process, the minimum Ti+V of Ti and V must be 〇.〇1%, and the excess must be added to > C and N. Therefore, the content must satisfy the range of (Ti + V) / (C + N) gl6 in terms of mass%. Preferably, Ti+V is set to be more than 5%. On the other hand, if the THV exceeds 0_8%, the manufacturability is lowered, so the upper limit of 0 Ti+V is limited to 8%.

Nb and Zr also form a carbonitride in the same manner as Ti and v described above, and the solid solution (:, Ν#) present in the steel is fixed, and has an effect of improving the manufacturability of the high alloy steel. X can be used as The action of the solid solution strengthening element is effective in high tensile strength and high fatigue strength. Therefore, in the inventions (3) and (4), it is also possible to use these elements instead of Ti^. In order to make c, _ = start to settle stably in the middle of the process. The minimum must contain the total Nb+Zl^G.G1% of Yb tZr. In addition, since C and N must be added to the excess, the content must be equal to (10) sand ((10) ^10的干〇〇 another, on the one hand, its mkj-7 j. (10) From λ b+zr more than 0.5%, the manufacturability will be reduced, so Nb+Zr is limited to 〇. 5〇/〇. - ί , Ti and v, and Nb and Zr form the yttrium as a carbonitride, and have the same effect as a solid solution-enhanced bismuth. Therefore, it can also be compounded to contain 312XP/invention specification (Supplement Na Grandma 147〇48 25 1312371 4 In this case, in order to make c and n start to settle stably in the middle of the manufacturing step, the minimum Ti+V+ of Ti, V, Nb, and Zr must be contained. Nb+Zr is 〇. 〇l%, and since c and N are required to be sufficiently excessively added, the content must be satisfied by mass% (Ti+V+Nb+Zr)/(C+N) -^16. However, if Ti+V+Nb+Zr exceeds 〇. 5%, the manufacturability is lowered, so Ti+V+Nb+Zr is limited to 〇. 5%. Also, ensure that it is not recrystallized. In order to restore the structure to the effect of high strength and magnetic properties, Τι is superior to Nb, V, and Zr. Therefore, in the present invention (1) and (2), it is necessary to add T i. 氺Μη : 3. 0% or less Μη It is an effective element for strengthening strength by solid solution, and is also an effective element for improving hot brittleness, and it is preferable to add 〇. 〇3% or more. However, since excessive addition causes deterioration of iron loss, the amount of addition is limited to 3 〇% or less. * Α1 : 3. 0% or less Α1 can be used as a strong deoxidizer, and it can improve the resistance of steel to reduce iron loss. It is also effective in strengthening strength by solid solution strengthening. However, excessive addition causes a decrease in the rolling property, so it is limited to 3.0%. It is preferably 2.0% or less. It is mainly used for strengthening by rabbits without recrystallization. In the inventions (1) and (2), it is preferable to set it as si+A^d. Further, the A1 is not necessarily included. For example, the addition of A1 may be suppressed below, that is, for example, deoxidation by Si. The reduction of M-face can also reduce the iron loss due to the decrease of precipitates such as A1N. However, the amount of A1 in the steel can be reduced in Yugong 312XP/Invention Manual (supplement)/96-03/95147048 26 1312371 The lower limit is 〇. 〇〇〇1%.氺P : 0. 2% or less Since P can obtain a large solid solution strengthening energy at a relatively small addition amount, it is extremely effective for high strength, and it is preferable to add 〇. 5% or more. However, it will be embrittled due to segregation, resulting in grain boundary cracks and reduced rolling properties. Therefore, the amount of addition should be limited to less than 2%, preferably less than 2%, and only in industrial steel. The lower limit of the amount that can be reduced is 〇〇〇1%.

氺s : 0.01% or less X If a phantom is present, a sulfide such as MnS is formed, which lowers the magnetic properties. : 者 MnS has the concern of becoming the starting point of fatigue damage. Therefore, steel " is best to reduce it as much as possible, but it is tolerable within 0 01%, so it is added as 〇·0.01% or less. # ‘The lower limit of the amount of s in the steel in the industry is about 0.0003%. _ *Other basic components of the non-oriented electrical steel sheet of the present invention may be added separately or in combination as well as conventionally modified n, ^, %, β, ", rare earth elements (Rem) And Co.: The amount of the body and the amount of lanthanum added must be harmless to the purpose of the present invention. Specifically, the rabbit τ 4+, 々々m and Λ η Λ 9 Λ , 疋 is the following target circumference. Sb : 0.002 ~ 〇 .1%, Sn: 0.002~0.1%, β: q 〇〇1~〇〇· 001^0.01%A c〇: '〇2^'〇〇/Γν , *〇〇1^〇1%'Rem is Good) ..〇% and Νι:5·0% or less (to ojj 〇! Especially to add N i is better. Also g. ^ Most of the elements, due to the hardening read solid solution strengthening and high electricity four 〖, Addition causes a decrease in saturation magnetic flux density, phase _ 312XP / invention specification (supplement) / 96 · 〇 3 / 95 ΐ 47 〇 48 27 1312371 where Ν ι does not reduce the saturation magnetic flux density to enhance the strength by solid solution strengthening And it is an extremely effective element for reducing iron loss due to high resistance. However, Ni is an expensive element. Excessive addition will cause an increase in cost, so it is preferable to contain 5.0% or less. - Again, the rest of steel unit The composition is Fe and unavoidable impurities. Inevitable impurities, in addition to the above-mentioned elements (which are inevitably contained for reasons of cost), Cu (using recycled steel as a raw material) In the case of the present invention, the reason for the limitation of the steel sheet structure in the present invention (1) and (2) is explained. In order to achieve the object of the present invention which combines high strength and magnetic properties, The steel sheet structure is preferably a composite structure. If the processed structure in the state after A rolling, the magnetic properties are remarkably deteriorated. On the other hand, if recrystallization is performed by final annealing, the magnetic properties are good and the strength is greatly lowered. In contrast, the recovery structure can be formed by annealing at about 500 C or more, and the recovery structure has high strength and can obtain relatively good magnetic properties. In the present invention (1), (2), effective It is important to use this recovery structure in order to balance the strength and magnetic properties, and the recovery structure of this ν'σ must be 50% or more in the cross-sectional observation of the steel sheet. # Further, in the present invention (3), (4) ), due to solid solution As a major strengthening institution, it is not necessary to ensure that the organization is not recrystallized. Therefore, as long as the strength can be ensured, the recrystallized structure is 1%%, and stable industrial productivity can be ensured. However, it is not excluded to use Reinforced Reinforced Tissue Strengthening 312ΧΡ/Invention Manual (Supplement)/96-03/95147048 28 1312371 Application [Manufacturing Method] Finally, the manufacturing method according to the present invention will be described, and the reasons for its limitation will be described. In the invention, the manufacturing step from the steel melting to the cold rolling can be carried out in accordance with a method generally employed for a general non-oriented electrical steel sheet. In particular, the present invention has a problem of having a C, N amount, and a carbonitride-forming element, even if the hot-rolled steel coil has a problem of the passability and the cold-rollability of the steel sheet. In the case of steel, the manufacturability can be greatly improved, so that it can be applied to the manufacturing steps of a general non-oriented electrical steel sheet. An example of a representative manufacturing method will be given below. First, a molten steel of a predetermined component is melted by a converter, a secondary refining, or an electric furnace, and is formed into a slab by a continuous casting method or a block-blocking method. Then, the flat steel chain is subjected to hot rolling, and the final temperature and the winding temperature in the hot rolling are not particularly specified, and general conditions can be used, for example, final rolling temperature: 700 ° 0900 ° C and winding temperature: The degree of 400 ° C ~ 800 ° C. • Then, if necessary, hot-rolled sheet annealing may be performed at a temperature of 600 to 1100 °C for the purpose of softening the steel sheet or improving the magnetic properties of the final product. After the hot-rolled sheet is annealed (after the hot-rolled sheet is annealed, it is after winding), cold rolling or warm rolling is performed to obtain a predetermined product sheet thickness (final sheet thickness). Further, the final thickness can be obtained by one-time cold rolling or warm rolling, or cold rolling or hot rolling in which the intermediate annealing is performed twice or more to obtain the final thickness. Further, the warm rolling is usually carried out at a sheet temperature of 100 to 300 °C. 315XP/发明发明(补件)/96-03/95147048 29 1312371 Further, the final thickness is preferably 0.15mm or more. That is, the plate thickness has a large influence on the magnetic properties of the product, particularly in the case of use as a rotor material for high-speed rotation, and has a large influence on the iron loss characteristics in a high frequency region of several hundred Hz or more. Thicker is better. On the other hand, as a result of examining the influence of the thickness of the product on the mechanical properties, fatigue properties and magnetic properties, the mechanical properties in the tensile test are hardly affected by the thickness of the sheet, and the fatigue characteristics are thinner than 0.15 mm. It will be drastically reduced. Further, if excessively thinned, in the motor manufacturing step, an increase in the number of steps 10 of the press or an increase in the number of layers may result in a disadvantage in productivity. Therefore, the lower limit of the sheet thickness is preferably set to 0.15 。. Further, the upper limit of the thickness of the sheet can be appropriately determined depending on the level of magnetic properties required, and is usually 0.65 mm or less as the user of the electromagnetic steel sheet. Further, in the present invention, as the magnetic properties due to the increase in strength are deteriorated, the conventional high-strength electromagnetic steel sheets are preferably suppressed, so that the same strength level and thickness can be obtained. The steel has better magnetic properties. ® Then, the final annealing and annealing conditions are carried out in a continuous annealing furnace, and there are individual regulations in the inventions (1), (2) and inventions (3) and (4). In the invention, (1), (2), the inner tension of the steel strip per unit area (the cross-sectional area of the cross section perpendicular to the direction of the steel sheet (so-called TD direction) is maintained at 2. 5MPa or more and 20MPa or less, and The most important one is the temperature range of 700 ° C or more and 850 ° C or less. By performing the final annealing on the rolled steel coil composed of the steel composition of the present invention under the above conditions, the non-recrystallized recovery structure remains in the steel sheet, and both the magnetic properties and the high strength can be considered, and the 312XP/invention specification (complement) Pieces) /96-03/95147048 30 1312371 A full steel coil shape correction effect can be exerted. That is, if the annealing temperature is less than 700 ° C or the tension is less than 2. 5 MPa, the shape bridge cannot be sufficiently performed. On the other hand, if it exceeds 85 baht. Oh, the strength is lowered due to the progress of recrystallization. Further, if the internal tension of the furnace exceeds 2 〇 liver &, the steel coil will locally deform, and the shape will be deteriorated or the furnace will be broken. Therefore, 20 MPa is used as the upper limit. From the viewpoint of the improvement of the shape of the steel sheet, a better operating range is the final annealing temperature of 75 (rc above 85 〇. 〇 below the furnace tension of 5 MPa or more and 15 MPa or less) and the final annealing temperature of the annealing strip #, to control the Recrystallization back, the area ratio of the structure is preferably 5% or more. The above annealing conditions substantially satisfy the requirement, and the amount of Ti in the steel is less than G 3%, and the maximum line retreat = degree TO:) 'based on It can be more surely ensured that the non-recrystallized recovery structure is considered to be 5iUu, so that the estimated value of Fig. 1 can roughly satisfy the following formula TS 850-16G (G.3-X) (where x = the amount of Ti in steel) On the other hand, in the inventions (3) and (4), the final annealing temperature is performed at a fire temperature of 70 (TC or more in the range of 1 G5 (rc or less). Recrystallization cannot be sufficiently performed, and recrystallization is not performed. Second, too much, the shape correction is not sufficient. χ, the magnetic properties can be determined: good. As the annealing temperature increases, the iron loss characteristics will also be improved = ", and 'mechanical properties (resistance, tensile strength) and Fatigue special = two retreats required magnetic characteristics level and strength water = Tian also decided The commercial frequency (9) ~ (four) z) to several kHz iron loss characteristics of the point of view, to _ ~ delete. c is better: to 312XP / invention manual (supplement) / 96 side 5147 〇 48 31 1312371 925 ~ 1025 ° C However, if the final annealing temperature exceeds 1050 ° C, not only the improvement of magnetic properties, but also the mechanical properties are reduced, and energy is also consumed, so the upper limit is limited to 1050 ° C. Immediately after the aforementioned final annealing, In the coating and baking treatment of the treatment liquid, the steel sheet coating is applied to form a final product. The type, thickness, and application conditions of the insulating coating film may be within a normal range. For example, a phosphate system may preferably be used. [Examples] _ (Example 1: Inventions (1), (2)) The flat steels of the compositions shown in Table 1 were subjected to hot rolling to 2.5 Torr, and then maintained at 900 ° C. After annealing for 60 seconds, the hot-rolled sheet is annealed and cold-rolled to a thickness of 0.35 mm. Here, since the amount of Ti exceeds the range of the present invention, the steel G has many spot defects after cold rolling, so Then, the subsequent treatment is carried out. Further, the amount of Si is as high as 4.3%, and the steel N containing almost no Ti exceeds the amount of Si. In the steel P of the scope of the invention, since the steel sheet was broken during cold rolling, the subsequent treatment was not carried out. Then, the final annealing of the soaking time of 20 seconds was carried out under the conditions shown in Table 2. Further, the tension in the furnace was The measurement was carried out by an in-furnace tensiometer which was attached to the lower part of the bearing by a load cell (1 oad ce 11). 312XP/Invention Manual (Supplement)/96-03/95147048 32 1312371 [Table 1]

Steel chemical composition (% by mass) Ti/(C+N) Si Μη A1 PS c N Ti C+NA 2.8 0.45 0.35 0.01 0.001 0.0025 0.0023 0.0009 0.0048 0.2 B 2.8 0.44 0.36 0.01 0.002 0. 0012 0.0018 0.056 0.0030 18.7 C 2.9 0.42 0.35 0.02 0.005 0. 0017 0.0019 0.14 0.0036 38.9 D 2.9 0.44 0.36 0.01 0.001 0.0045 0.0033 0.35 0.0078 44.9 E 2.8 0.52 0.35 0.02 0.002 0.0008 0.0015 0.55 0.0023 239.1 F 3.4 0.05 0.001 0.01 0.0004 0.0023 0.0031 0.75 0.0054 138.9 G 2.9 0.05 0.001 0.01 0. 0015 0.0018 0.0022 0.88 0.0040 220.0 Η 2.9 0.05 0.001 0.01 0. 0015 0.0020 0.0020 0.73 0.0040 182.5 I 2.8 0.42 0.36 0.02 0.002 0.0021 0.0022 0.062 0.0043 14.4 J 2.8 0.40 0.36 0.02 0.002 0.0048 0.0076 0.55 0.0124 44.4 K 2.9 0.06 0.001 0.01 0.001 0.0025 0.0026 0.41 0.0051 80.4 L 3.8 0.07 0.001 0.01 0.001 0.0023 0.0028 0.40 0.0051 78.4 Μ 4.3 0.05 0.001 0.01 0.0005 0.0024 0.0026 0.41 0.0050 82.0 N 4.2 0.05 0.001 0.01 0.0008 0.0025 0.0025 0.0005 0.0050 0.1 0 3.3 0.45 1.0 0.02 0.001 0.0032 0.0023 0.42 0.0055 76.4 P 5.2 0.05 0.001 0.01 0. 00 05 0.0028 0.0022 0.41 0.0050 82.0 Q 1.8 2.0 1.0 0.12 0.001 0.0013 0.0015 0.20 0.0028 71.4 R 1.8 2.0 1.0 0.12 0.001 0.0012 0.0016 0.03 0.0028 10.7

312XP/Invention Manual (Repair)/96-03/95147048 33 1312371 The mechanical properties of the steel sheet thus obtained were evaluated by JIS No. 5 tensile test piece cut in parallel with the rolling direction, and the magnetic properties were taken. The rolling direction and the direction perpendicular to the rolling direction were evaluated by the same number of Epstein test pieces. Then, the steel sheet was cut in the rolling direction, and the thickness section thereof was polished to observe the structure, and the ratio of the area of the recrystallized structure was determined. For the microstructure at a final annealing temperature of 500 ° C or higher, the area excluding the recrystallized portion is regarded as the ratio of the recovery structure. Further, the measurement and evaluation results of the flatness of the steel sheet before and after annealing before and after annealing were measured in accordance with JIS C2550 and are shown in Table 2.

312XP/Invention Manual (supplement)/96-03/95147048 34 1312371 [Table 2]

Steel G: Many spots are formed during cold rolling, and the steel N and P which have not been treated subsequently are broken due to cold rolling, so the subsequent processing is not performed 312XP/»W#(»)/96 -〇3/95147048 35 1312371 2 Γ : Using the steel A of the conventional composition as the material after rolling, 〇. /, annealing temperature at the recovery temperature of the steel (400 ° C) 2: 〇: 2' is composed of 1% of processed tissue. Although the tensile strength is high, the shellfish is deteriorated. In addition, Νο·3 and n〇.4, which are annealed at 60 (TC~6), have high strength, and the iron loss also has a tendency to change. However, the flatness is hardly improved before and after annealing. On the other hand, the area ratio of unrecrystallized grains is less than 5 (10) and X and % aa are the main defects. 5 and i 5b 'the strength is significantly reduced. ^Steel in the steel I No. 33 and No. 41, which are 16 times higher than c+N, fail to obtain sufficient strength; N?34 having a C+N exceeding 〇〇1〇% has a high iron loss. In contrast, the steel of the present invention is used. Invention example of steel composed of the composition

No. 6 15 17~19, 32, 35~38 and 40, showing high strength and low iron loss, and excellent in steel plate shape. Further, the amount of Si in the steel exceeds 4.0%, and the amount of No. 37 and Si+Al exceeds 4.0%. The bending characteristics after annealing of No. 38' hot rolled sheet are 27 times and 23 times, respectively. On the other hand, in the other invention examples, it is 4 times or more, and the manufacturability is more excellent. Here, the bending property is a bending radius i5 mm and a bending angle 90 at a temperature of 30 °C. The repeated bending test was carried out to evaluate the number of cracks in the steel sheet. (Example 2: Inventions (1), (2)) The slabs of steels A and D of Table 1 were hot rolled to 2 mm, and then subjected to annealing at 80 (Tc kept for 6 sec.). After pickling and cold rolling to a thickness of 35 mm, a steel coil was produced. The obtained steel coil was subjected to final annealing in a continuous annealing furnace under the conditions shown in Table 3, and was carried out in the same manner as in Example 1 12XP/Invention Manual (Supplement ()) /96-03/95147048 36 1312371 The same evaluation. The results are also shown in Table 3. It can be seen from Table 3: steel a and D, at a lower annealing temperature of 65 (TC, even if the furnace tension is increased, steel plate The degree of improvement in shape is also small. On the other hand, the annealing temperature is increased to 8 〇〇t, and the shape of the steel sheet of the steel coil in which the furnace tension is controlled within the range of the present invention is remarkably improved. In contrast, the steel D of the present invention can achieve both high strength and excellent steel sheet shape by annealing, and the furnace tension exceeds the upper limit of the appropriate range by 20 MPa. The iron loss increases and the shape of the steel plate also deteriorates.

312XP/Invention Manual (supplement)/96-03/95147048 37 1312371 [Table 3]

No. Steel No. Final annealing temperature (°C) Furnace tension (MPa) Iron loss Wl0/400 (W/kg) Tensile strength TS (MPa) Recovery structure ratio (%) Recrystallization structure ratio (%) Before annealing Flatness (%) Flatness after annealing (%) Remarks 20 A 650 5 40. 1 704 65 35 3.6 3.1 Comparative Example 21 A 650 15 39.5 701 63 37 3.6 2.8 Comparative Example 22 A 800 5 22. 5 550 0 100 3.5 1.9 Comparative Example 23 A 800 15 21. 7 548 0 100 3.6 1.4 Comparative Example 24 D 650 5 61.3 998 100 0 3.4 3.1 Inventive Example 25 D 650 20 62.3 1009 100 0 3.4 2.6 Invention Example 26 D 800 1.5 32.3 681 78 22 3.4 2.8 Inventive example (manufacturing method not suitable) 27 D 800 5 32.1 688 77 23 3.3 2.0 Inventive example 28 D 800 10 31.9 685 75 25 3.4 1-7 Inventive example 29 D 800 15 31.9 679 78 22 3.4 1.6 Inventive example 30 D 800 20 32.5 682 78 22 3.4 1.6 Invention Example 31 D 800 23 37.8 680 78 22 3.4 2.2 Inventive example (manufacture method is not suitable)

312XP/Invention Manual (Supplement)/96-03/95147048 38 1312371 (Example 3: Invention (1), (2)) The slabs having the compositions shown in Table 4 were cooled under the conditions of a to c below. Roll to the final thickness. a: After hot rolling to a thickness of 2. Omm, without hot-rolled sheet annealing, the temperature is rolled to the final thickness of 0. 35mm (plate temperature 250 ° C) b: hot rolling to plate thickness 3. After 8 mm, the hot rolled sheet is annealed, cold rolled to 1.5 mm, and then subjected to intermediate annealing at 1 000 ° C for 30 seconds, and then cold rolled to a final thickness of 0.35 mm. After the thickness of the sheet was 2. 5 mm, the hot rolled sheet was annealed at 1,050 ° C for 30 seconds, and then cold rolled to 1.01 mm, and then subjected to intermediate annealing at 1000 ° C for 30 seconds. The temperature was rolled (plate temperature: 200 ° C) to a final thickness of 0.20 mm. Then, the final annealing was performed for 10 seconds on the soaking time under the conditions shown in Table 5, and the same evaluation as in Example 1 was carried out, and the results were recorded together in the table. 5. Each of the steels of the present invention has excellent strength and magnetic properties.

312XP/Invention Manual (supplement)/96-03/95147048 39 1312371 [Table 4] Steel chemical composition (% by mass) Ti/(C+N) Si Μη A1 PS c N Ti C+N Other S 2.8 0.45 0. 35 0. 01 0.001 0. 0020 0.0018 0.35 0.0038 Ni: 3.4 92.1 T 2.8 0.44 0.35 0.01 0.001 0.0021 0.0020 0.36 0.0041 Sb: 0.08 87.8 U 2.8 0.45 0.34 0.02 0.001 0. 0022 0.0017 0.35 0.0039 Sn: 0.03 89.7 V 2.8 0.46 0.34 0 01 0.002 0.0019 0. 0022 0.33 0.0041 B: 0.002 Ca: 0. 002 80.5 W 2.8 0.45 0.36 0. 01 0.001 0. 0023 0.0018 0.35 0.0041 Sb: 0.05 REM: 0.004 85.4 X 2.8 0.45 0.35 0.01 0.001 0.0022 0.0019 0.34 0.0041 Co : 2.5 82.9 Y 2.8 0.43 0.35 0.01 0.001 0. 0020 0. 0019 0.35 0.0039 Ni: 4.3 Sn: 0.08 B: 0.003 89.7

[table 5]

No. Steel No. Rolled cake final CC) Furnace m (MPa) Iron loss Wl just (W/kg) Tensile strength TS (MPa) Responsibility ratio (%) Recrystallization ratio (°/〇) Flat Secret (%) 耿 (%) 42 S a 800 10 33.5 768 77 23 3.8 2.0 Inventive Example 43 T a 770 10 35 785 89 11 3.9 2.2 Inventive Example 44 ua 850 10 32 707 60 40 3.9 1.8 Inventive Example 45 V b 800 15 33 772 74 26 3.9 2.0 Inventive Example 46 wb 720 15 42 840 100 0 3.6 2.0 Inventive Example 47 XC 780 15 28 855 88 12 4.1 1.9 Inventive Example 48 YC 720 15 25 924 100 0 4.2 2.1 Inventive Example 312 XP/Invention Manual (Supplement) /96-03/95147048 40 1312371 (Example 4: Invention (3), (4)) The flat steel of the composition shown in Table 6 was hot rolled to 2 mm and then at 900 °. After annealing for 60 seconds, the hot rolled sheet was annealed and then cold rolled to a sheet thickness of 0.35 mm, and then held at 950 ° C for a final annealing of 30 seconds. At this time, the hot-rolled annealed sheet was cut into a width of 30 mm, and a re-bending bending test was performed at a temperature of 30 ° C with a bending radius of 15 mm and a bending angle of 90 ° to carry out the steel sheet passability of the manufacturing line. Simulation evaluation. The edge crack depth of the end face of the aforementioned hot rolled annealed sheet was measured as an evaluation of cold rolling property. The mechanical properties (tension resistance TS), fatigue characteristics (fatigue ultimate strength FS), and magnetic properties (magnetic flux density B5 〇, high-frequency iron loss Wl 0/1 00 0 ) of the thus obtained electromagnetic steel sheet were examined. In Table 7. Further, the evaluation method of each characteristic is as follows. The mechanical properties were evaluated using a JIS No. 5 tensile test piece. The fatigue characteristics were evaluated by cutting the test piece in parallel with the rolling direction. After the parallel end face was ground with 800 grit sandpaper, the stress ratio was 0.11. Frequency: 20 Hz partial stretching (stretching-stretching) ), the maximum stress (fatigue limit strength FS) at which no plate fracture occurred after 10 million (107) cycles was evaluated. The magnetic properties were evaluated by the same number of Epstein test pieces in the rolling direction and perpendicular to the rolling direction. 312XP/Invention Manual (Repair)/96-03/95147048 41 1312371 [Table 6] Chemical composition of steel (Quality Magic (Ti+V) /(C+N) Si Μη A1 Ni P sc N C+N Ti V 1 4.21 0.05 0 0 0.01 0.001 0.0018 0. 0023 0. 0041 0.001 0 0^2 2 4.18 0.05 0 0 0.01 0. 002 0.0019 0. 0025 0. 0044 0.01 0 2^3 3 4. 20 0. 04 0 0 0. 02 0.002 0. 0017 0. 0022 0. 0039 0.05 0 12.8 4 4.20 0.05 0 0 0.01 0.001 0.0015 0.0023 0. 0038 0.071 0 18.7 5 4.11 0.04 0 0 0.02 0.002 0.0019 0. 0028 0. 0047 0.15 0 31.9 6 4. 29 0.04 0 0 0.01 0.002 0. 0022 0. 0026 0. 0048 0.31 0 64.6 7 4.11 0.05 0 0 0.01 0.001 0. 0024 0. 0022 0. 0046 0.49 0 106.5 8 4.10 0.06 0 0 0.01 0.002 0.0022 0.0024 0. 0046 0.75 0 163.0 9 4.21 0.06 0 0 0.01 0.001 0.0019 0.0021 0.0040 1.19 0 297.5 10 4.19 0.05 0 0 0.01 0.002 0. 0042 0. 0035 0. 0077 0. 0005 0 11 4.10 0. 04 0 0 0.02 0.002 0. 0044 0. 0036 0 0080 0. 04 0 5J 12 4.20 0. 04 0 0 0.01 0.001 0. 0038 0. 0038 0. 0076 0.08 0 10.5 13 4.11 0.04 0 0 0.02 0.002 0. 0041 0. 0040 0. 0081 0.12 0 14.8 14 4.10 0.05 0 0 0.01 0.001 0. 0048 0. 0044 0. 0092 0.198 0 21.5 15 4.21 0.06 0 0 0.01 0.002 0. 0047 0. 0039 0. 0086 0.31 0 36.0 16 4.10 0. 05 0 0 0.01 0.002 0.0048 0. 0033 0.0081 0.7 0 86.4 17 4.31 0. 06 0 0 0.01 0.001 0. 0044 0. 0030 0. 0074 0.92 0 124.3 18 4.11 0.06 0 0 0.01 0.002 0.0042 0. 0034 0. 0076 1.48 0 194.7 19 4.21 0.06 0 0 0.01 0.002 0.0153 0. 0035 0.0188 0.0007 0 0.0 20 4.10 0. 04 0 0 0.02 0.001 0.0148 0. 0038 0.0186 0. 04 0 2J, 21 4. 29 0. 04 0 0 0.01 0.002 0.0155 0. 0041 0.0196 0.11 0 5^6 22 4.10 0. 05 0 0 0.02 0. 002 0.0152 0. 0045 0.0197 0.195 0 9,_9 23 4.19 0. 05 0 0 0.01 0. 001 0.0151 0. 0046 0.0197 0.35 0 17.8 24 4.10 0. 04 0 0 0.01 0.002 0.0148 0. 0049 0.0197 0.77 0 39.1 25 4.12 0. 04 0 0 0.01 0.001 0.0152 0. 0038 0.0190 0. 95 0 50.0 26 4. 28 0.05 0 0 0.01 0.002 0. 0144 0.0031 0.0175 1.25 0 71.4 27 4.12 0.06 0 0 0. 01 0. 002 0.032 0. 0033 0. 0353 0.0008 0 〇28 4.20 0. 04 0 0 0.02 0.001 0.033 0. 0028 0. 0358 0.098 0 2J_ 29 4. 20 0.05 0 0 0.01 0.002 0. 035 0. 0041 0. 0391 0.2 2 0 5^6 30 4.28 0.06 0 0 0.01 0. 002 0.032 0. 0044 0. 0364 0.43 0 11.8 31 4.11 0. 05 0 0 0.02 0.001 0.033 0. 0041 0. 0371 0.62 0 16.7 32 4.19 0.04 0 0 0.01 0 002 0.033 0. 0036 0. 0366 0.82 0 22.4 33 4.11 0.04 0 0 0. 02 0.002 0.031 0. 0046 0. 0356 1.03 0 28.9 58 3.22 0.05 0 0 0.01 0.001 0. 0025 0. 0022 0. 0047 0.48 0 102.1 59 3. 71 0.05 0 0 0.01 0.001 0. 0024 0. 0024 0. 0048 0.48 0 100.0 312XP / invention manual (supplement) /96-03/95147048 42 1312371 [Table 7]

Bending times of hot-rolled steel sheets (times) Depth of cracks at the edge of cold-rolled sheets (mm) TS (MPa) FS (MPa) ΒδΟ (T) WlO/lk (W/kg) Remark 1 4.0 3.7 621 528 1.69 78 Comparative example 2 3.8 1.4 630 529 1.69 79 Comparative Example 3 8.2 1.1 671 570 1. 67 83 Comparative Example 4 24.5 0.4 669 575 1.67 84 Inventive Example 5 28.8 0.2 697 599 1.66 86 Inventive Example 6 29.0 0.3 756 643 1.64 92 Inventive Example 7 31.0 0.4 825 701 1.63 96 Inventive Example 8 28.0 0.4 919 772 1.60 104 Inventive Example 9 8.5 5.0 1090 850 1.56 122 Comparative Example 10 3.0 5.4 632 525 1.69 83 Comparative Example 11 3.0 4.1 635 545 1.67 88 Comparative Example 12 5.5 3.5 695 570 1.66 95 Comparative Example 13 10.4 1.3 735 610 1.66 96 Comparative Example 14 23.9 0.7 755 634 1.65 99 Inventive Example 15 24.8 0.5 799 687 1.64 106 Inventive Example 16 26.5 0.7 950 808 1.60 119 Inventive Example 17 9.0 0.6 1050 872 1.58 129 Comparative Example 18 7.0 5.6 1220 1000 1.52 159 Comparative Example 19 1.0 9.0 638 523 1.68 95 Comparative Example 20 0.5 9.0 680 537 1.67 117 Comparative Example 21 2.0 6.2 715 551 1.64 144 Comparative Example 22 2.6 5.0 791 593 1.61 153 Comparative Example 23 7.2 3.5 853 631 1.59 161 Comparative Example 24 11.9 3.1 1006 734 1.55 180 Comparative Example 25 6.2 4.8 1080 778 1.53 182 Comparative Example 26 3.9 6.8 1195 848 1.50 191 Comparative Example 27 1.0 9.0 651 508 1.67 118 Comparative Example 28 0.5 9.0 733 535 1.64 159 Comparative Example 29 1.4 9.0 855 581 1.61 190 Comparative Example 30 0.5 5.8 1000 610 1.59 224 Comparative Example 31 3.4 4.5 1065 660 1.57 229 Comparative Example 32 7.2 4.3 1138 694 1.55 239 Comparative Example 33 1.5 6.7 1218 706 1.53 243 Comparative Example 58 76 0.1 587 464 1.66 117 Comparison Example 312XP 762 609 1.65 101 Inventive Example 312XP/Invention Manual (Supplement)/96-03/95147048 43 1312371 As shown in Table 7, it is known that Si is more than 3.5%, and the amount of C and N is in accordance with the present invention. The invention examples of controlling and adding an appropriate amount of T i have excellent manufacturability, high tensile strength and fatigue limit, and good magnetic properties can be obtained. (Example 5: Inventions (3), (4)) The hot-rolled steel sheet having the composition shown in Table 8 was hot rolled to a thickness of 2 mm, and then held at 900 ° C for 60 seconds. After the annealing, pickling was carried out, followed by cold rolling to a sheet thickness of 0.25 Å, followed by final annealing at 950 ° C for 30 seconds. • At this time, the hot rolled annealed sheet was cut to a width of 30 mm, and a reverse bending test was performed at a temperature of 30 ° C with a bending radius of 15 mm and a bending angle of 90 ° to carry out a simulation evaluation of the steel sheet passability on the manufacturing line. The edge crack depth of the rolled end face was measured as an evaluation of the cold rolling property. The mechanical properties (tension resistance TS), fatigue characteristics (fatigue ultimate strength FS), and magnetic properties (magnetic flux density B5 〇, high-frequency iron loss W10/l) of the electromagnetic steel sheet thus obtained were examined, and the results were shown. In Table 9.

312XP/Invention Manual (supplement)/96-03/95147048 44 1312371 [Table 8] (Ti+V) /((10) 傩Main Si Μη A1 Ni P sc NC€ Ti V period also 34 3.62 0.12 0 0 0.01 0.001 0.0111 0.0028 0.0139 0.058 0.045 - 1Λ ttfef column 35 3.68 0.11 0 0 0.01 0.002 0.0015 0.0023 0.0038 0.52 0 & 1: 0.025 136.8 Griffin J 36 3.90 0.13 0 0 0.02 0.002 0.0019 0.0028 0.0047 0.52 0 - 110.6 Steel chest 37 411 0.14 0 0 0.01 0.001 0.0024 0.0022 0.0046 0.49 0 - 106.5 38 462 0.13 0 0 0.02 0.002 0.0022 0.0015 0.0037 0.50 0 Ca: 0.0018 135.1 Mine column 39 489 0.11 0 0 0.01 0.002 0.0022 0.0019 0.0041 0.51 0 — 1214 Weng Lie 40 5.20 0.14 0 0 0.01 0.001 0.0024 0.0022 0·_ 0.52 0 - liao ttfei column 41 5.62 0.12 0 0 0.01 0.002 0.0022 0.0024 0.0046 0.75 0 - i6a o _ column 42 a7i 2,10 0 0 0.01 0.001 0.0019 0.0021 0.0040 0.35 0 B:0.0012 87.5 Side column 43 3.69 0.05 1.82 0 0.01 0.002 0.0015 0.0035 0.0050 0.35 0 - 70.0 44 a68 0.04 0 1.91 0.02 0.002 0.0019 0.0015 0.0034 0 0.55 - 161.8 Outline 45 3.71 0.04 0 a22 0.01 0.001 0.0024 0.0019 0.0043 0.25 0.34 S b: 0.095 137.2 Side 歹丨 J 46 3.70 0.04 0 489 0.02 0.002 0.0011 0.0024 0.0035 0.73 0 〇D: 1.21 2〇a6 Side column 60 411 0.14 0 0 0.01 0.001 0.0033 0.0035 0.0068 0.04 0.05 - ia2 _ column 61 411 0.14 0 0 0.01 0.001 0.0034 0.0033 0.0067 0.04 0.30 — 50.7 Gue 62 411 0.14 0 0 0.01 0.001 0.0033 0.0034 0.0067 0.40* 0.50* - 1343 t tender column * *) Ti+V>0· 8% 312XP/invention manual (supplement)/ 96-03/95147048 45 1312371 [Table 9]

Bending times of hot-rolled steel sheets (times) Depth of cracks at the edge of cold-rolled sheets (mm) TS (MPa) FS (MPa) ΒδΟ (T) WlO/lk (W/kg) Remark 34 6.4 4.7 602 457 1.69 115 Comparative example 35 37 0.2 765 650 1.65 71 Inventive Example 36 34 0.6 790 672 1.64 72 Inventive Example 37 32.5 0.7 795 684 1.64 72 Inventive Example 38 27.5 0.9 843 717 1.62 72 Inventive Example 39 19 0.9 870 731 1.61 77 Inventive Example 40 5.3 2.9 910 564 1.60 81 Comparative Example 41 2.2 5.4 1025 574 1.57 85 Specific Example 42 15.2 0.6 764 634 1.65 102 Inventive Example 43 22.2 0.5 778 661 1.59 63 Inventive Example 44 26 0.7 769 661 1.65 61 Inventive Example 45 23.3 0.5 840 772 1.64 69 Inventive Example 46 20.5 0.4 957 818 1.63 72 Invention Example 60 5.5 6.4 631 538 1.68 74 Specific vehicle example 61 28.3 0.8 736 604 1.65 72 Invention Example 62 3.5 5.1 1010 688 1.51 86 Comparative example

312XP/Invention Manual (Supplement)/96-03/95147048 46 1312371 As shown in Table 9, it is understood that the steel sheet component is controlled to satisfy the C and N amounts of the present invention, and an appropriate amount of Ti and V is added. In the invention examples, all of them have excellent manufacturability, high tensile strength and fatigue limit, and good magnetic properties can be obtained. On the other hand, if the Si addition amount exceeds 5%, the bendability and cold-rollability of the hot-rolled sheet are greatly lowered, and the fatigue ultimate strength tends to decrease despite the high tensile strength. (Example 6: Invention (3), (4)) The slab having the composition shown in Table 10 was hot rolled to a thickness of 2.2 mm, and then maintained at 80 ° C for 90 seconds. After the hot rolled sheet was annealed, it was pickled, then cold rolled to a sheet thickness of 0.30 mm, and then subjected to final annealing at 1000 ° C for 30 seconds. 5毫米(板温度280°C)-> 900°C, except for No. 67, the hot-rolling annealing is omitted, and the hot-rolling is performed to a thickness of 3. 0 mm - no hot-rolled sheet annealing - > -30 seconds intermediate annealing - cold rolling to a final sheet thickness of 0.30 轧制 rolling step. Further, the hot-rolled annealed sheet (No. 67 is a hot-rolled sheet) was cut into a width of 30 mm, and a reverse bending test was performed at a temperature of 30 ° C with a bending radius of 15 匪 and a bending angle of 90° to carry out a steel sheet on the manufacturing line. Simulation of passability. The edge crack depth of the rolled end face was measured as an evaluation of the cold rolling property. The mechanical properties (tension resistance TS), fatigue characteristics (fatigue ultimate strength FS), and magnetic properties (magnetic flux density B5, high-frequency iron loss W10/100) of the thus obtained electromagnetic steel sheets were examined, and the results are shown in Table 11. . 312XP/Invention Manual (Supplement)/96-03/95147048 47 1312371 [Table 10] Chemical composition (% by mass) (Nb+Zr)/(C+N) Remarks Si Μη A1 Ni P sc N C+N Nb Zr Ti V Other 47 4.51 0.11 0.32 0 0.02 0.002 0.0008 0.0015 0.0023 0.014 0 0 0 - 6J _Example 48 4.62 0.12 0.32 0 0.01 0.002 0.0009 0.0013 0.0022 0.076 0.008 0 0 Ca: 0.0030 38.2 Inventive Example 49 4.53 0.11 0.34 0 0.02 0.001 0.0015 0.0025 0.0040 0.16 0.05 0 0 _ 52.5 Inventive Example 50 4.51 0.14 0.35 0 0.01 0.001 0.0019 0.0025 0.0044 0.42 0 0 0 Sn: 0.082 95.5 Inventive Example 51 4.58 0.15 0.33 0 0.02 0.002 0.0022 0.0019 0.0041 0.68 0.15 0 0 - 202.4 Comparative Example 52 4.43 0.10 0.28 0.5 0.01 0.002 0.0031 0.0010 0.0041 0.03 0 0.17 0 - 48.8 « Inventive Example 53 4.43 0.13 0.32 0 0.01 0.001 0.0021 0.0025 0.0046 0 0.15 0.10 0.10 - 76.1 « Inventive Example Sn: 0.05 REM: 63 4.20 0.10 0.28 0.2 0.01 0.001 0.0022 0.0023 0.0045 0.10 0.10 0.10 0.10 0.002 88.9« Inventive Example Ca: 0.002 64 4.20 0.10 0.28 0.2 0.01 0.001 0.0036 0.0040 0.00 76 0.04 0.03 0 0 - i2 65 4.20 0.10 0.28 0.2 0.01 0.001 0.0035 0.0038 0.0073 0.05 0.04 0 0 - 12.3 Invention Example 66 4.20 0.10 0.28 0.2 0.01 0.001 0.0036 0.0039 0.0075 0.30 Wood 0.30* 0 0 - 80.0 _ Example 67 4.43 0.10 0.28 0.5 0.01 0.002 0.0031 0.0010 0.0041 0.03 0 0.17 0 a 48.8« Invention example

*) Nb+Zr>0.5°/〇 **) (Ti+V+Nb+Zr)/(C+N)

312XP/Invention Manual (supplement)/96-03/95147048 48 1312371 [Table 11] Bending times of hot rolled steel sheets (times) Edge cracking depth of cold rolled sheets (mm) TS (MPa) FS (MPa) ΒδΟ (T) WlO/lk (W/kg) Remark 47 2.5 5.0 678 502 1.66 71 Comparative Example 48 23.6 1.2 706 551 1.65 73 Invention Example 49 22.1 0.9 758 599 1.64 74 Invention Example 50 17.1 1.7 862 672 1.61 74 Invention Example 51 6.2 6.3 1055 749 1.55 82 Comparative Example 52 16.5 0.9 855 668 1.61 76 Inventive Example 53 12.0 0.9 887 691 1.60 77 Inventive Example 63 26.5 0.4 808 701 1.62 76 Inventive Example 64 1.0 12.5 576 389 1.62 78 Comparative Example 65 18.3 0.6 723 586 1.62 74 Inventive Example 66 6.5 4.5 660 461 1.55 83 Comparing with the car 67* 43.5 0.4 903 710 1.58 78 Inventive example

*) Hot-rolled to sheet thickness 3. No hot-rolled sheet annealing - Warm rolling to a sheet thickness of 1.5 mm (plate temperature 280 ° C) 900 ° C - 30 seconds intermediate annealing -> Cold rolling to final sheet thickness 0. 30iran

312XP/Invention Manual (Supplement)/96-03/95147048 49 1312371 · As shown in Table 11, the steel sheet composition is controlled to satisfy the C and N amounts of the present invention, and the optimum Nb, Zr or Ti is added, The invention examples of V have excellent manufacturability, high tensile strength and fatigue limit, and good magnetic properties. - (Example 7: Inventions (3), (4)) The composition of the steel composition of the present invention is 3.9% Si, 0.14% Mn, 0.33% A1, 2.67% Ni, 0.02% P, 0.002%S, 0.0009%C, 0. 0018M, 0. 28%Ti and 0. 055Sn Lu slab consisting of (Ti/(C+N) = 103. 7), hot rolled to a thickness of 2 mm The hot-rolled sheet was annealed at 1000 ° C for 60 seconds, then subjected to pickling, followed by cold rolling to various thicknesses, and then subjected to final annealing at 950 ° C for 30 seconds. Check the impact of each feature. The results obtained are shown in Table 12.

312XP/Invention Manual (supplement)/96-03/95147048 50 1312371 [Table 12] Steel plate thickness (mm) TS(MPa) FS(MPa) Bs〇(T) WlO/lk(W/kg) Remarks 54 0.35 776 667 1.65 91.0 Inventive Example 55 0.20 781 656 1. 65 52.4 Inventive Example 56 0.15 769 638 1. 65 44.2 Inventive Example 57 0.11 782 555 1.65 39.4 Inventive Example (outside the scope of application)

312XP/Invention Manual (Repair)/96-03/95147048 51 1312371 As shown in Table 12, the plate thickness is made high-frequency iron loss. Moreover, the tensile strength can be greatly improved. However, the fatigue limit is substantially the same under the thickness of the plate. (Industrial Applicability - The above is remarkably improved. According to the present invention, the composition of the hunting component is defined by the limited component or the second step, and the fatigue property is excellent without increasing the limitation on the manufacture of the steel sheet and the additional steps. The non-directional steel plate is also excellent in the magnetic properties of the plate. Unit =. 〇 and recrystallization rate (number in circle: unit = area relationship. ' Figure 2 shows the steel plate in the steel (C + N) amount (abscissa: unit = mass %) The graph of the influence of the passability (the number of bends X ordinate: unit = number of times). For example, Figure 3 shows the amount of (C+N) in the steel (abscissa: unit = mass%) versus cold rolling (rolling) The curve of the influence of the edge crack depth X ordinate: unit = mm) of the end face of the plate. Figure 4 shows the amount of Ti in the steel under the amount of (c + Ν) of four kinds of grades (horizontal coordinates: unit = Mass %) influence on the passability (bending times) (ordinates: unit = number of times) of the steel sheet of the manufacturing line Fig. 5 is a graph showing the passability (bending times) of the steel plate of the manufacturing line in the Ti/(C+N) ratio (abscissa) of the four levels of steel (C + Ν) (the ordinate) The graph of the influence of the unit = the number of times. 312XP / invention manual (supplement) / 96-03 / 95147048 52 1312371 f 6 is the amount of η in the steel (c + n) in the steel of the four levels ( Plate coordinates: unit = mass %) A graph of the effect of cold rolling properties (edge cracking of the edge of the rolled sheet) (ordinate: unit = mm). Figure 7 shows the steel in four levels ( C + N) The amount of Ti / (c + 趵 ratio on the cold rolling properties (edge crack depth of the end of the rolling plate) ( = color) curve. Early figure 8 is shown in four kinds of steel The graph of the influence of Ti amount (abscissa: unit = mass%) against tension (ts) (abscissa: unit = MPa) in steel under medium (C+N) amount. Figure 9 shows the results at four levels. The graph of the influence of Ti amount (abscissa: unit = mass %) on the fatigue limit (FS) (abscissa: unit =) in the steel under the amount of (C+N) in steel. Figure 10 shows the four levels. The amount of Ti in steel under the amount of (c+N) in steel ( Coordinates: unit = mass %) A graph of the effect of high-frequency iron loss (w 10/1000) (ordinate: unit = W/kg). Also, in Figures 4 to 10, ♦ is c+N: 0 · 0038~0. 〇〇48% by mass, _ is 〇+, 0.0074~0.0092% by mass, ^ is 〇+, 0.0175~0.0196% by mass, X is C+N: 0. 0353~0. 0391% by mass. 312XP /Invention manual (supplement)/96-03/95147048 53

Claims (1)

1312371 X. Patent application scope: 1. A high-strength non-oriented electrical steel sheet characterized in that its composition is: by mass%: C and N: C is 〇. 〇1〇% or less and N is 〇 〇1〇% or less, and suppressed to C+N^ 〇. 010% ; Si · 1.5% or more and 5.0% or less; Μη : 3. 0% or less; A1 : 3. 0 % or less; > P : 0. 2% or less; and S: 0.01% or less; further, 3 has Ti. 0.05% or more and 0.8% or less, and satisfies the range of Ti/(c+N) 2 16; the rest is Fe and not Impurities to avoid; and the ratio of the presence of the non-recrystallized recovery structure in the steel sheet is an area ratio of 5〇% φ 2. As claimed in the patent scope 〇· 01% and Co : 〇. 2~5. 0%. High-strength non-directional electromagnetic steel »i · 1.5% or more and 4·〇% or less. 2 high-strength non-directional electromagnetic steel 4. A strength-free non-oriented electrical steel sheet characterized in that its composition is, in mass%, contains: 54 312XP/invention specification (supplement)/96-〇3 / 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 : 3. 0% or less; Α1 : 3. 0% or less; Ρ : 0. 2% or less; and S: 0.01% or less 'or further containing Ni: 5.0% or less; and 'containing either Ti or V Or two kinds of 'the total is above on% and below 0.8%' and satisfy the range of (Ti+v)/(C+N)216; the rest is Fe and unavoidable impurities. 5. A high-strength non-oriented electrical steel sheet characterized by having a composition of, in mass%, C: N and C are 〇. 〇1〇% or less and n is 〇. 〇1〇% or less And is determined to be C+N^0.010%; Si: more than 3.5% and 5.0% or less; Μη: 3. 0% or less; Α1: 3·0% or less; Ρ: 0.2% or less; and S: 0. 01% or less, or further containing Ni: 5. 〇% or less; and containing either or both of Mb and Zr, the total of which is ο·% or more and 0·5% or less, and is satisfied. (Nb+Zr)/(C+N) g 10 range; the rest is Fe and unavoidable impurities. 6. A high-strength non-oriented electrical steel sheet characterized in that its composition is in mass% The meter contains: 312XP/invention specification (supplement)/9 dip 3/95147048 55 1312371 C and N: C is 0. 010% or less and N is 〇. 010% or less, and is set to C+N ^ 0.010%; Si: more than 3.5% and 5.0% or less; Μη: 3. 0% or less; -Α1: 3. 0% or less; Ρ: 0·2% or less; and S: 0.01% or less, or further containing Ni : 5.0% or less; in addition, at least 1 of Ti and V With ribs, at least 丄 种 ' ' 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 01 The high-strength non-oriented electrical steel sheet according to any one of claims 4 to 6, further comprising a group selected from the group consisting of the following: 1 or more; in terms of mass%: 0. 002~0. 1%, Sn: 0.002~0.1%, BGGG1~〇.〇l%, Ca: 0.001~0.01%, Rem: I 0.00b 0.01% and Co: 0.2 to 5.0%. 8. A method for producing a high-strength non-oriented electrical steel sheet, characterized in that hot flat steel having the following composition is hot rolled and then cooled After the annealing temperature is 7 〇 (rc or more and 85 〇 or less, and the furnace internal tension is 2. 5 MPa or more and 20 MPa or less, after the final annealing is performed. The final annealing; ' 312XP / invention specification (supplement) / 96-03 / 95147048 56 1312371 The above composition is contained in mass %: C and N: C is 〇. 010% or less and N is 〇. 〇1〇% or less, and suppressed to ^0. 010%; 'Si: 1. 5% or more and 5. 〇% or less; Μη : 3 · 0 % or less; A1 : 3 · 0% or less; P : 〇·2 mass% or less; _S: 0.01% by mass or less; further containing: 0.05% by mass or more and 〇8% by mass or less, and satisfying the range of Ti/(C+N) g 16 . 9. A method for producing a non-oriented electrical steel sheet having a strength, characterized in that, after hot rolling of a slab having the composition shown in any one of items 4 to 7 of the patent application, hot rolling is performed as needed The sheet is annealed, and then subjected to cold rolling or warm rolling, or by cold rolling or warm rolling in which the intermediate annealing is performed twice or more, thereby forming a final sheet thickness, and then at an annealing temperature of 70 ( The method of producing a high-strength non-oriented electrical steel sheet according to claim 9 wherein the final thickness is 0.15 mm or more. 312XP/Invention Manual (supplement)/96_03/95147〇48 57