Title of the invention: Non-oriented electrical steel sheet and a method for manufacturing a laminated core using the non-oriented electrical steel sheet.
Technical field
[0001]
　The present invention relates to a non-oriented electrical steel sheet and a method for manufacturing a laminated core using the non-oriented electrical steel sheet, and more particularly to a non-oriented electrical steel sheet having excellent continuous punching property.
Background technology
[0002]
　In the fields of electrical equipment, especially rotating machines, small and medium-sized transformers, electrical components, etc., in which non-oriented electrical steel sheets are used as the core material, there is an increasing demand for higher efficiency and smaller size.
　Regarding the reduction of iron loss among the performance characteristics of non-oriented electrical steel sheets, a method of increasing the content of Si, Al, etc. has generally been adopted from the viewpoint of reducing eddy current loss due to an increase in electrical resistance. Various improvement techniques have been proposed for increasing the magnetic flux density.
　On the other hand, when a non-oriented electrical steel sheet is used as an iron core of a rotating machine or the like in an electric device, it is necessary to consider a change in magnetic characteristics during processing. In particular, when a non-oriented electrical steel sheet is punched as an iron core material, the shape of the punched end face and the crimped portion not only affects the iron core performance, but also affects the stackability and formability of the iron core. .. That is, unless the iron core is formed into a predetermined shape, the magnetic properties as a material of the non-oriented electrical steel sheet cannot be exhibited.
[0003]
　Various non-oriented electrical steel sheets having excellent magnetic properties as a material for an iron core of an electric device and also having excellent punching workability for facilitating molding into an iron core of an electric device have been proposed.
[0004]
　Patent Document 1 relates to non-oriented electrical steel sheets having excellent punching workability and high yield stress (400 MPa or more), and in terms of mass%, Si: 1.5% or more and 3.5% or less, Mn: 1. .5% or less, Al: 0.2% or more and 3.0% or less, Mg: 0.0003% or more and 0.0050% or less, or Ti: 0.0010% or more and 0.010% or less, C: It contains 0.0010% or more and 0.010% or less, and is composed of the balance Fe and unavoidable impurities. The crystal grain size d of the product plate is 5 μm or more and 40 μm or less, and the relationship of d ≦ 50 × (Si + 0.5Al-2) is established. Non-oriented electrical steel sheets characterized by filling are disclosed.
[0005]
　Patent Document 2 aims to provide a non-oriented electrical steel sheet having excellent strength without sacrificing yield and productivity in punching of a motor core and steel sheet production, in terms of mass%, C: 0.01. % Or more and 0.05% or less, Si: 2.0% or more and 4.0% or less, Mn: 0.05% or more and 0.5% or less, Al: 3.0% or less, Nb: 0.01% or more and 0 It contains 0.05% or less, consists of the balance Fe and unavoidable impurities, the content of Mn and C is mass% and satisfies Mn ≤ 0.6-10 × C, and the area ratio of the recrystallized portion of the steel sheet is 50. % Or more, a non-oriented electrical steel sheet characterized in that the yield strength in a tensile test is 650 MPa or more, the breaking elongation is 10% or more, and the iron loss W10 / 400 is 70 W / kg or less is disclosed.
[0006]
　Patent Document 3 aims to provide a non-oriented electrical steel sheet having excellent punching workability that facilitates molding into an iron core of an electric device, and has a C: 0.003% or less and a Si: 1.0% or more. It contains 3.0% or less, Al: 0.1% or more and 3.0% or less, Mn: 0.1% or more and 1.0% or less, and satisfies 0.2 ≦ Al / (Si + Al) ≦ 0.6. Disclosed are non-oriented electrical steel sheets having a steel component composed of the balance Fe and unavoidable impurity elements, a yield ratio of 0.6 or more, and a Vickers hardness of 200 or less.
[0007]
　Patent Document 4 describes C: 0.05% or less and P: 0.2% or less in mass% in order to solve the problem that the plate bends or bends when punched into the shape of the core. , Si: 5% or less, Mn: 5% or less, Al: 3% or less, S: 0.02% or less and N: 0.01% or less, and the ratio of the X-ray integrated reflection intensity to the theoretical intensity P (hkl). ) ((Hkl) is the orientation of the (hkl) plane in the plate surface), TP value = P (222) / P (200) is 1.3 or more, and the recrystallization rate is 20% or less. The non-directional electromagnetic steel plate is disclosed.
Prior art literature
Patent documents
[0008]
Patent Document 1: Japanese Patent Application Laid-Open No. 2005-113158
Patent Document 2: Japanese Patent Application Laid-Open No. 2008-050685
Patent Document 3: Japanese Patent Application Laid-Open No. 2011-140683
Patent Document 4: Japanese Patent Application Laid-Open No. 2008-202070
Outline of the invention
Problems to be solved by the invention
[0009]
　Most of the iron cores for drive motors of eco-cars such as EVs (electric vehicles) and HEVs (hybrid vehicles) are laminated bodies (laminated cores) of thin non-oriented electrical steel sheets with a thickness of 0.30 mm or less. The continuous punching method using a mold is widely adopted as a highly productive method. Recently, there is a tendency to increase the continuous punching speed (the transport speed of the steel sheet during progressive punching) in order to further improve the productivity. However, in the non-directional electromagnetic steel plates described in Patent Documents 1 to 4, the steel plate being transported is separated from the transport surface and the horizontal plane on which the punching mold is installed during high-speed punching (the plate is in the transport direction on the transport surface). It may flutter in the vertical direction perpendicular to the above), and it is necessary to reduce the transport speed, which not only hinders the improvement of productivity, but also causes troubles in the punching process if it is not properly transported to the punching position. It was also found that the productivity was greatly reduced.
[0010]
　An object of the present invention is to provide a non-oriented electrical steel sheet and a method for manufacturing a laminated core using the non-oriented electrical steel sheet, which can improve the above-mentioned transportability of the steel sheet even when continuously punching at high speed.
Means to solve problems
[0011]
　It was presumed that the buckling strength of the steel sheet was insufficient as the cause of the deterioration of the transportability of the steel sheet when continuous punching was performed at high speed using the non-oriented electrical steel sheet. Then, in order to improve the buckling strength, it was conceived that it is effective to set both the yield strength and Young's modulus of the steel sheet to high values. Furthermore, it was found that this effect is likely to be exhibited in steel grades having a relatively high Mn or C content.
[0012]
　When both the yield strength and Young's modulus of the steel sheet were set to high values ​​in the steel sheet whose Mn and C contents were specified based on the above estimation, the transportability of the steel sheet could be improved when continuously punching at high speed. It was.
[0013]
　The present invention has been made based on the above findings, and the gist thereof is as follows.
[1] In mass%, Si: 2.0 to 5.0%, Mn: 0.4 to 5.0%, Al ≦ 3.0%, C: 0.0008 to 0.0100%, N ≦ 0 It contains .0030%, S ≤ 0.0030%, Ti ≤ 0.0060%, the balance is composed of Fe and unavoidable impurities,
　and the product of the contents of Mn and C is 0.004 to 0.05% by mass 2 .
　A non-directional electromagnetic steel sheet that is within the range, has a yield strength of 600 MPa or more in the rolling direction, and has a Young's modulus of 200 GPa or more in the rolling direction.
[2] The non-oriented electrical steel sheet according to [1], further containing 0.001 to 0.50% in total of one or more of Ni, Cr, Mo, Sn, and Sb in mass%. ..
[0014]
[3] When a laminated core is manufactured using a progressive die using the non-oriented electrical steel sheet having excellent continuous punching property according to [1] or [2] as a material, the transfer speed of the steel sheet is V (m / s). ) Satisfies the following equation (1), a method for manufacturing a laminated core.
[0015]
　V: V MIN to V MAX　　　　　　　　　　　　　(1)
　V MAX = (1/25) √ (t 2 x E x YS) (2)
　V MIN = (1/25) √ (t 2 x 120,000) (3)
However, t: Thickness of electromagnetic steel sheet (mm), E: Young's modulus of electromagnetic steel sheet in rolling direction (GPa), YS: Yield strength of electromagnetic steel sheet in rolling direction (MPa)
[4] The manufactured laminated core is 750 to 900 ° C. The method for producing a laminated core according to [3], which is characterized by strain removal and annealing.
Effect of the invention
[0016]
　According to the present invention, by setting the yield strength of the non-directional electromagnetic steel sheet in the rolling direction to 600 MPa or more and the Young's modulus in the rolling direction to 200 GPa or more, the transportability of the steel sheet can be improved when continuously punching at high speed.
Mode for carrying out the invention
[0017]
　All of the inventions described in Patent Documents 1 to 4 aim at improving the punching property of a steel sheet. Patent Document 1 has a problem that the steel sheet becomes brittle as the strength increases and the productivity and yield deteriorate remarkably as punching property, and the material does not cause embrittlement while having a yield stress of 400 MPa or more. Is presented. Patent Document 2 presents a punching property having a problem that the punched motor core is cracked and the yield and productivity are deteriorated, and the yield strength is 650 MPa or more and the breaking elongation is 10% or more. .. Patent Document 3 aims to form a punched end face, a crimped portion, or the like into a predetermined shape as an iron core as punching property, and has a yield ratio of 0.6 or more and a Vickers hardness of 200 or less. I am presenting it. Patent Document 4 has a problem as punching property that when punching is performed into the shape of a core, it becomes difficult to transport the steel sheet for laminating after punching due to breakage during punching, and the steel plate can be freely placed in a cantilever state. The amount of sagging at the edge is measured, and the one with less sagging is presented.
[0018]
　On the other hand, in the case of high-speed punching, which is the object of the present invention, it has been found for the first time that the problem of transportability of the steel sheet to the punching position is not the problem of deterioration of transportability after punching due to breakage during punching. .. The non-oriented electrical steel sheet having excellent continuous punching property, which is the subject of the present invention, means a non-oriented electrical steel sheet having excellent transportability to a punching position at the time of continuous punching.
[0019]
　Then, as a result of detailed examination by the present inventor, in order to obtain a non-directional electromagnetic steel sheet having excellent transportability to the punched position at the time of continuous punching, which is the object of the present invention, the rolling direction of the steel sheet It was found for the first time that the yield strength of the steel sheet is required to be 600 MPa or more and the Young's modulus in the rolling direction is 200 GPa or more. By improving the yield strength to 600 MPa or more, the elastic range of the material can be widened, thereby avoiding breakage during transportation. At the same time, by setting the Young's modulus to 200 GPa or more, deformation in the elastic region can be reduced, and fluttering (vibration) of the steel sheet due to device vibration, resonance, or the like can be suppressed. The yield strength is preferably 620 MPa or more, more preferably 715 MPa or more. The Young's modulus is preferably 205 GPa or more, more preferably 210 GPa or more. As for the "yield strength" defined in the present invention, "0.2% proof stress" is defined as "yield strength" for a steel sheet in which an upper yield point does not appear in a tensile test. Further, in the steel sheet in which the upper yield point appears in the tensile test, the "upper yield point" is defined as the "yield strength". Further, the method for measuring "Young's modulus" defined in the present invention is not particularly limited, and a known measuring method is used. Specifically, "Young's modulus" is obtained from the slope of the elastic deformation region showing a linear relationship in the displacement-load curve obtained in a normal tensile test.
　The yield strength and Young's modulus here are those at the time of punching and are measured with an electromagnetic steel sheet with a film. The changes in yield strength and Young's modulus caused by the coating are negligible and negligible.
[0020]
　Next, the reason for limiting the steel component of the present invention will be described. In addition,% means mass%. The Si, Mn, Al, C, N, S, and Ti content ranges of the steel sheet of the present invention are not significantly different from the conventional component composition range known as non-oriented electrical steel sheets. In particular, it is characterized in that the contents of Mn and C are controlled within a specific range.
[0021]
　Si is a component that has the effect of reducing iron loss by increasing electrical resistance and reducing eddy current loss. In order to exert this effect, it is necessary to contain 2.0% or more. On the other hand, if the content increases, the magnetic flux density decreases and the cost increases, so the content is set to 5.0% or less.
[0022]
　When Mn is contained together with C, it has an effect of suppressing flapping of the steel sheet at the time of high-speed punching. To obtain the effect, the Mn content is set to 0.4% or more. Further, Mn has the effect of increasing the electric resistance to reduce the eddy current loss, improving the primary recrystallization texture, reducing the hysteresis loss, and improving the magnetic flux density. If the Mn content is too large, the crystal grain growth property itself at the time of annealing is lowered and the hysteresis loss is increased, so the content is set to 5.0% or less. The Mn content is preferably 1.0% or more and 4.6% or less, more preferably 1.6 to 4.2%, still more preferably 2.2 to 3.8%.
[0023]
　When C is contained together with Mn, it has an effect of suppressing flapping of the steel sheet at the time of high-speed punching. To obtain the effect, 0.0008% or more is required. However, when the content exceeds 0.0100%, iron loss deterioration due to magnetic aging becomes remarkable. It is preferably 0.0021 to 0.0090%, more preferably 0.0041 to 0.0080%.
[0024]
　Further, the contents of Mn and C shall be such that the product of each content is in the range of 0.004 to 0.05% by mass 2 . If the product is less than 0.004, it is considered that the interaction between Mn and C as described below does not work, and a sufficient invention effect cannot be obtained. The upper limit of the product is determined from the upper limit of each of the above elements. The range is preferably 0.006 to 0.04% by mass 2 , and more preferably 0.008 to 0.03% by mass 2 .
[0025]
　The reason why the effect of the present invention is exhibited when Mn and C coexist at a relatively high concentration is not clear, but is considered as follows. It is known that Mn and C have an interaction (so-called Mn—C dipole) that attracts each other in steel, and has an effect of suppressing long-distance diffusion of C. On the other hand, C is known to have a vibration suppressing effect due to internal friction. In the present invention, it is presumed that Mn suppresses the long-distance diffusion of C and amplifies the vibration suppressing effect via internal friction caused by the short-distance movement of C. The effect is presumed to be a synergistic effect due to the combination of dislocations (lattice defects) and C's attractive interaction in addition to the attractive interaction between Mn and C.
[0026]
　Like Si, Al is also a component that has the effect of reducing iron loss by increasing electrical resistance and reducing eddy current loss, increasing the ratio of magnetic flux density to saturated magnetic flux density and improving magnetic flux density. It also works. If the Al content is too large, the saturation magnetic flux density itself decreases, which leads to a decrease in the magnetic flux density. Therefore, the Al content is set to 3.0% or less. The Al content is preferably 0.1% or more, but Al may not be contained.
[0027]
　N is 0.0030% or less because it produces a nitride and deteriorates the iron loss property. Since S forms sulfide and deteriorates the iron loss property, it is set to 0.0030% or less. Ti produces various precipitates such as TiN, TiS, and TiC, which not only deteriorates the iron loss property but also completely fixes C, which is considered to play an important role in the present invention, as a carbide. Since it eliminates the useful effect on the effect of the invention, it is set to 0.0060% or less.
[0028]
　The non-oriented electrical steel sheet of the present invention may further contain at least one of Ni, Cr, Mo, Sn, and Sb in a mass% of 0.001 to 0.50% as a selective component. Ni, Cr, Mo, Sn, and Sb each affect the formation of a recrystallized texture and exert a significant effect on improving the magnetic properties of the steel sheet, and these effects are exhibited at a content of 0.001% or more. On the other hand, if the content is too large, the effect on the recrystallized texture plate is saturated, so the upper limit of the content is set to 0.50% in total.
[0029]
　The method for manufacturing the non-oriented electrical steel sheet of the present invention will be described.
The non-directional electromagnetic steel sheet of the present invention can be produced by a normal process consisting of steelmaking, hot rolling (or hot rolling, hot rolling sheet annealing), pickling, cold rolling, and finish annealing. The production conditions for hot rolling do not require any special conditions. For example, the slab heating temperature for hot rolling may be 1000 to 1200 ° C., and the winding temperature may be 700 ° C. or lower as standard conditions. No special conditions are required for cold rolling.
[0030]
　In the production of the steel sheet of the present invention, the yield strength and Young's modulus can be kept within the range of the present invention by adjusting the conditions of finish annealing. By lowering the finish annealing temperature to, for example, 740 ° C. or lower, both the yield strength and Young's modulus can be increased. On the other hand, if the finish annealing temperature is too low, the flatness of the steel sheet may be poor. Therefore, for a steel sheet having the component composition of the present invention, the finishing annealing temperature that satisfies the yield strength and Young's modulus of the present invention can be determined for each component composition while maintaining good flatness of the steel sheet.
[0031]
　Further, in particular, controlling the cooling rate of finish annealing has an advantageous effect on the manifestation of the effects of the present invention. Specifically, the average cooling rate in the temperature range of 600 to 100 ° C. may be 60 ° C./s or less, and the average cooling rate CR1 in the temperature range of 600 to 350 ° C. is 40 ° C./s or less, 350 to 100 ° C. It is preferable that the average cooling rate CR2 in the temperature range is 40 ° C./s or more and CR2-CR1> 0 ° C./s. More preferably, CR2-CR1 ≧ 20 ° C./s. The reason why such a cooling pattern is preferable is not clear, but the effect is seen in the steel sheet of the present invention containing a predetermined amount of Mn and C, and it is particularly effective in increasing Young's modulus, which affects the short-distance movement of C. It is considered that there is a relationship with the interaction between Mn and C, which exerts a vibration suppressing effect.
Probably, when the average cooling rate is set to 40 ° C./s or less at 350 ° C. or higher, Mn-C pairs are generated by the diffusion of C, and the vibration suppression effect during steel sheet transportation can be obtained, whereas at 350 ° C. or lower, the average cooling rate is obtained. If the speed is less than 40 ° C./s, it is presumed that carbides are generated from the Mn—C pair and the vibration suppression effect is lost.
[0032]
　When high-speed punching was performed using the non-oriented electrical steel sheet of the present invention, a test was conducted to see how much the transfer speed of the steel sheet could be increased.
　Here, the transport speed of the steel sheet is the time required for purely transporting the steel sheet, not including the time required for punching, and is obtained by dividing the transport distance. This is because the steel sheet is stationary when the steel sheet is punched in the high-speed punching process. Generally, the transport speed of this steel sheet is about 1.1 to 1.5 times the total punching speed (calculated including the time required for punching and the time for purely transporting the steel sheet) in the high-speed punching process. Is.
[0033]
　A non-oriented electrical steel sheet having components such as Si: 3.2%, Mn: 1.0%, Al: 0.7%, balance Fe and unavoidable impurities in% by mass was produced. By adjusting the plate thickness to 0.10 to 0.30 mm through hot rolling and cold rolling and changing the finish annealing temperature after cold rolling, the yield strength is between 350 and 850 MPa, and the Young's modulus is 170 to 230 GPa. Manufactured the steel plate between.
　The plate width of the steel plate is not particularly limited, but the plate width is set to 300 mm to 500 mm in consideration of handling with a general punching device.
　Generally, the thinner the steel sheet, the more likely it is that fluttering will occur during transportation. Therefore, the range of the thickness of the steel plate here is set from 0.25 mm, which is a general thickness, to 0.10 mm, which is relatively thin.
[0034]
　For high-speed punching, the transport speed was varied within the range of 1 to 4 m / s when the laminated core was manufactured using the progressive die.
[0035]
　As a result of the test, the limit of the transport speed (V MAX ) of the steel sheet capable of performing continuous punching without causing fluttering is the plate thickness, Young's modulus and yield when the yield strength and Young's modulus of the steel sheet are within the above range of the present invention. It was found that it can be expressed by a specific function of intensity ((1/25) √ (t 2 × E × YS)). That is, it was found that the transportability in high-speed punching is good when the transport speed V (m / s) of the steel sheet does not exceed the V MAX obtained by the following equation (2) .
　V MAX = (1/25) √ (t 2 × E × YS) (2)
However, t: Thickness of electrical steel sheet (mm), E: Young's modulus in rolling direction of electrical steel sheet (GPa), YS: Electromagnetic steel Yield strength (MPa) of steel sheet in rolling direction
[0036]
　On the other hand, when the yield strength and Young's modulus are the lower limits of the present invention, the yield strength is 600 MPa and the Young's modulus is 200 GPa, the V MAX of the above equation (1) is (1/25) √ (t 2 × 120,000). It is possible to operate with the upper limit of the transport speed. From the opposite point of view, it can be said that the steel sheet of the present invention is characterized in that the transport speed can be increased to (1/25) √ (t 2 × 120,000) or more. In the present invention, the limit of the transport speed when the above-mentioned yield stress and Young's modulus are the lower limits of the steel sheet of the present invention is defined as V MIN .
　V MIN = (1/25) √ (t 2 x 120,000) (3)
[0037]
　Then, the invention is a method of continuously punching the steel sheet of the present invention in a range of a transport speed of V MIN or more and V MAX or less, that is, a method of manufacturing a laminated core satisfying the formula (1).
　V: V MIN to V MAX　　　　　　　　　　　　　(1)
　That is, in the method for manufacturing a laminated core of the present invention, the steel sheet of the present invention whose material is appropriately controlled is used, and a high-speed transfer speed, which was difficult in the past, is appropriately adopted. It becomes possible to perform continuous punching. As a matter of course, in actual operation, the conveying speed of the steel sheet in the punching step, V MIN be lower than, the transport of such flutter problems do not occur. As an example, when the processing speed of the steps before and after the punching step is rate-determining, the transport speed in the punching step may be lower than VMIN .
[0038]
　It should be noted that even a steel sheet that does not satisfy the yield strength and Young's modulus required by the steel sheet of the present invention has a range of transport speeds specified by the above-mentioned V MIN and V MAX . For example, even if Young's modulus is too low to satisfy the present invention, if only the yield strength is sufficiently high, the value of V MAX will be sufficiently higher than V MIN , and the transport speed satisfying the equation (1). Will exist. However, such a steel sheet causes a problem in transportability even if the transport speed is within the range of the formula (1). This is because it is necessary to satisfy both the yield strength and Young's modulus at the same time in addition to the steel component in order to realize the effect of the present invention.
[0039]
　After manufacturing a laminated core using the non-oriented electrical steel sheet of the present invention, the manufactured laminated core is strain-removed and annealed at 750 to 900 ° C. in order to obtain a core with less iron loss. As a result, the strain of the manufactured laminated core disappears, the core iron loss is reduced, and a high-efficiency motor can be manufactured. If the strain-removing annealing temperature is less than 750 ° C., the crystal grain size of the steel sheet does not grow sufficiently and becomes fine particles. On the other hand, when the strain annealing temperature exceeds 900 ° C., the laminated steel sheets stick to each other and the core iron loss increases. Therefore, the strain removing annealing temperature was set in the range of 750 to 900 ° C. In the annealed atmosphere of strain relief annealing, it is preferable to reduce the oxidizing gas concentration.
Example
[0040]
　The molten steel melted in a converter is continuously cast to obtain a slab having the composition shown in Table 1, and hot rolling, hot rolling, annealing, and cold rolling are performed by a conventional method to obtain a plate thickness of 0.25 mm to 0. A 10 mm cold rolled plate was used. This cold-rolled plate was finish-annealed at the temperature and cooling rate shown in Table 1 to obtain a non-oriented electrical steel sheet, and a steel strip having a plate width of 410 mm was sampled by slitting. The finish annealing atmosphere was 100% nitrogen. For the manufactured non-oriented electrical steel sheets, the yield strength in the rolling direction and the Young's modulus in the rolling direction were measured and shown in Table 2. Reference example No. For 20 and 28, since the finish annealing temperature was too low and the flatness of the steel sheet was poor, the subsequent evaluation of high-speed punching property and the evaluation of iron loss were not performed. In all the examples, the N content was 0.0030% or less, the S content was 0.0030% or less, and the Ti content was 0.0060% or less.
[0041]
　Regarding the evaluation of high-speed transferability, when manufacturing a laminated core using a progressive die, the transfer speed is within the range of 2.0 to 4.0 m / s for a steel plate with a plate thickness of 0.25 mm, and the plate thickness is 0. The .15 mm steel sheet was varied within the range of 1.5 to 2.5 m / s, and the 0.10 mm steel sheet was varied within the range of 0.8 to 1.7 m / s. Regarding the evaluation of high-speed transportability, "○" was displayed in Table 2 as a good example in which normal punching and laminating could be performed without fluttering, and "x" was displayed in Table 2 as a defect in other cases. Examples of defective cores marked with "x" include poor shape such as a partial step in the stacking thickness direction of the laminated core, or core caulking (cracking) during post-process motor assembly. It is conceivable that the steel sheet is fluttered as a cause of the defective core. Flapping means that the steel sheet is deformed or buckled, so that the steel sheet separates in the vertical direction perpendicular to the horizontal plane on which the transport surface and the punching die are installed. Regarding the transportability, it was judged to be acceptable if no problem occurred at any transport speed of V MIN or less and V MAX or less. If a problem occurs at at least one of the transport speeds of V MIN or less and V MAX or less, it is judged as rejected and the “x” is underlined.
　In Table 2, No. In 1 to 19 (series with a plate thickness of 0.25 mm), the transport speed is 2.0 m / s and all are "○". For transport speeds slower than that, no problem occurs, so no test is performed. "-" Was displayed. Similarly, even in Nos. 21 to 27 (series with a plate thickness of 0.15 mm), if the transport speed is slower than 1.5 m / s, no problem will occur, so no test is performed and "-" is displayed. did.
[0042]
[table 1]

[0043]
[Table 2]

[0044]
　<< Plate Thickness 0.25 mm >>
　Example No. of the present invention. For 1 to 14, both the yield strength and Young's modulus were within the range of the present invention, and the high-speed transferability was good at a transfer rate of V MIN or more and V MAX or less. On the other hand, Comparative Example No. In No. 15, Mn × C was out of the scope of the present invention, and Comparative Example No. In 16 and 17, the finishing annealing temperature was too high, and one or both of the yield strength and Young's modulus were out of the scope of the present invention. Therefore, the calculated V MIN is higher than the V MAX . As a result , even at a transport speed of V MIN or less, a problem occurred in transportability. Comparative Example No. In 18 and 19, since Mn × C is out of the range of the present invention and Young's modulus is out of the range of the present invention , good transfer cannot be performed at a transfer speed of V MAX or less.
[0045]
　<< Plate Thickness 0.15 mm >>
　Example No. of the present invention. For 21 to 26, both the yield strength and Young's modulus were within the range of the present invention, and even if the transfer speed of the steel sheet was set to a high speed in the range of V MIN or more and V MAX or less, the high-speed transfer property was good. On the other hand, Comparative Example No. 27 deviates from Mn × C is the range of the present invention, the Young's modulus is outside the scope of the invention, V resulting MAX in the conveying speed in the range, resulting in a defect in conveyance property.
[0046]
　<< Plate Thickness 0.10 mm >>
　Example No. of the present invention. For 29 to 30, both the yield strength and Young's modulus were within the range of the present invention, and even if the transfer speed of the steel sheet was set to a high speed in the range of V MIN or more and V MAX or less, the high-speed transfer property was good.
[0047]
　A laminated core was manufactured from a member punched at the highest transport speed that did not cause any problems, and strain was removed and annealed at 800 ° C. Regarding the laminated core, the iron loss was evaluated as a pseudo ring by winding a B coil and an exciting coil around the back yoke portion, and the iron loss W 10/200 (W / kg) is shown in Table 2. If the iron loss W 10/200 is 5 W / kg or less, it is judged to be good. In both the examples of the present invention and the comparative examples, the iron loss was within the range where there was no problem in practical use, but the iron loss tended to be better in the examples of the invention. This is probably because the steel of the present invention has a likelihood up to the upper limit of the transport speed and the punching is good with an accuracy equal to or higher than the evaluation limit. It is considered that the change in crystal structure (crystal orientation and grain size) when the steel sheet was subjected to grain growth by strain annealing and annealing acted in a direction favorable for iron loss.
The scope of the claims
[Claim 1]
　By mass%, Si: 2.0 to 5.0%, Mn: 0.4 to 5.0%, Al ≤ 3.0%, C: 0.0008 to 0.0100%, N ≤ 0.0030% , S ≤ 0.0030%, Ti ≤ 0.0060%, the balance is composed of Fe and unavoidable impurities,
　and the product of the contents of Mn and C is in the range of 0.004 to 0.05% by mass 2.
　A non-directional electromagnetic steel sheet having excellent continuous punching property, characterized in that the yield strength in the rolling direction is 600 MPa or more and the Young's modulus in the rolling direction is 200 GPa or more.
[Claim 2]
　The non-directional, which is excellent in continuous punching property according to claim 1, further containing 0.001 to 0.50% in total of one or more of Ni, Cr, Mo, Sn, and Sb in mass%. Electrical steel sheet.
[Claim 3]
　When a laminated core is manufactured by using a progressive die using the non-oriented electrical steel sheet having excellent continuous punching property according to claim 1 or 2, the conveying speed V (m / s) of the steel sheet is as follows. A method for manufacturing a laminated core, which comprises satisfying the equation (1).
　V: V MIN to V MAX　　　　　　　　　　　　　(1)
　V MAX = (1/25) √ (t 2 x E x YS) (2)
　V MIN = (1/25) √ (t 2 x 120,000) (3)
However, t: Thickness of the electromagnetic steel sheet (mm), E: Young's modulus of the electromagnetic steel sheet in the rolling direction (GPa), YS: Yield strength of the electromagnetic steel sheet in the rolling direction (MPa)
[Claim 4]
　The method for manufacturing a laminated core according to claim 3, wherein the manufactured laminated core is strain-removed and annealed at 750 to 900 ° C.