Non-oriented electrical steel sheet and hot rolled steel sheet thereof

Abstract

A non-oriented electrical steel sheet having a high magnetic flux density and a low iron loss at not only a commercial frequency but also a high frequency zone, which has a chemical composition including C: not more than 0.0050 mass %, Si: more than 1.5 mass % but not more than 5.0 mass %, Mn: not more than 0.10 mass %, sol. Al: not more than 0.0050 mass, P: more than 0.040 mass % but not more than 0.2 mass %, S: not more than 0.0050 mass %, N: not more than 0.0040 mass % and Ca: 0.001-0.01 mass % and the remainder being Fe and inevitable impurities and a compositional ratio of CaO in oxide-based inclusions existing in a steel sheet of not less than 0.4 and/or a compositional ratio of Al.sub.2O.sub.3 of not less than 0.3, and a hot rolled steel sheet used as a raw steel material thereof.

Claims

1. A non-oriented electrical steel sheet having a chemical composition consisting of C: not more than 0.0050 mass %, Si: more than 1.5 mass % but not more than 5.0 mass %, Mn: not more than 0.10 mass %, sol. Al: 0.0001 mass % to not more than 0.0050 mass %, P: more than 0.040 mass % but not more than 0.2 mass %, S: not more than 0.0050 mass %, N: not more than 0.0040 mass %, Ca: 0.001-0.01 mass %, optionally Sn: 0.01 mass % to not more than 0.1 mass %, optionally Sb: 0.01 mass % to not more than 0.1 mass %, and the remainder being Fe and inevitable impurities, wherein, in oxide based inclusions in a finished form of the steel sheet, a mass % ratio as defined by equation (1) is not less than 0.4, and/or a mass % ratio as defined by equation (2) is not less than 0.3,
CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO)(1),
Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO)(2).

2. A hot rolled steel sheet used as a raw material for the non-oriented electrical steel sheet of claim 1, the hot rolled steel sheet having a chemical composition consisting of C: not more than 0.0050 mass %, Si: more than 1.5 mass % but not more than 5.0 mass %, Mn: not more than 0.10 mass %, sol. Al: 0.0001 mass % to not more than 0.0050 mass %, P: more than 0.040 mass % but not more than 0.2 mass %, S: not more than 0.0050 mass %, N: not more than 0.0040 mass %, Ca: 0.001-0.01 mass %, optionally Sn: 0.01 mass % to not more than 0.1 mass %, optionally Sb: 0.01 mass % to not more than 0.1 mass %, and the remainder being Fe and inevitable impurities, wherein, in oxide based inclusions in the hot rolled steel sheet, a mass % ratio as defined by equation (1) is not less than 0.4, and/or a mass % ratio as defined by equation (2) is not less than 0.3,
CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO)(1),
Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO)(2).

3. The non-oriented electrical steel sheet according to claim 1, wherein the steel sheet has a magnetic flux density (B.sub.50) that is not less than 1.69 T.

4. The non-oriented electrical steel sheet according to claim 1, wherein the steel sheet has a magnetic flux density (B.sub.50) that is not less than 1.70 T.

Description

BRIEF DESCRIPTION OF THE DRAWING

(1) FIG. 1 is a graph showing an influence of a compositional ratio of an oxide-based inclusion existing in a steel sheet upon a magnetic flux density B.sub.50.

EMBODIMENTS FOR CARRYING OUT THE INVENTION

(2) At first, the inventors have performed an experiment for examining an increase of a magnetic flux density through an improvement of a texture by using a steel slab of a chemical composition decreasing Mn and Al contents as far as possible and adding P and Sn and/or Sb with reference to the aforementioned conventional techniques, concretely a steel slab containing C: 0.0017 mass %, Si: 3.3 mass %, Mn: 0.03 mass %, P: 0.08 mass %, S: 0.0020 mass %, sol. Al: 0.0009 mass %, N: 0.0018 mass % and Sn: 0.03 mass %.

(3) However, when the above steel slab is heated to 1100 C. and then hot-rolled to a thickness of 2.0 mm, troubles such as cracking or breakage due to brittleness are caused in a part of the slabs. In order to elucidate the cause of the breakage, the broken steel sheet is examined on the way of the hot rolling and hence it has been found that S is concentrated in a broken portion. Since concentration of Mn is not observed in the S-concentrated portion, the cause of the brittleness is guessed due to the fact that S in steel forms FeS having a low melting point during the hot rolling.

(4) In order to prevent the brittleness due to the formation of FeS, it is enough to decrease S, but there is a limit in the decrease of S because desulfurization cost is increased. On the other hand, there is a method of suppressing the brittleness with S by adding Mn, but the addition of Mn becomes disadvantageous for the increase of the magnetic flux density.

(5) Now, the inventors have considered that when S is fixed as CaS and precipitated by adding Ca, the formation of liquidus FeS can be prevented to suppress the brittleness in the hot rolling and made the following experiment.

(6) When a steel slab comprising C: 0.0017 mass %, Si: 3.3 mass %, Mn: 0.03 mass %, P: 0.09 mass %, S: 0.0018 mass %, sol. Al: 0.0005 mass %, N: 0.0016 mass %, Sn: 0.03 mass % and Ca: 0.0030 mass % is reheated to a temperature of 1100 C. and hot-rolled to a thickness of 2.0 mm, cracking or breakage is not caused.

(7) From the above, it is understood that the addition of Ca is effective for preventing the cracking or breakage in the hot rolling.

(8) Then, the inventors have observed a section perpendicular to the rolling direction (C-section) in a hot rolled sheet produced by using the steel slab of the above chemical composition as a raw material and a product sheet (finishing-annealed sheet) with a scanning electron microscope (SEM) to analyze a chemical composition of oxide-based inclusions existing in the steel sheet and investigated a relation between the analyzed results and magnetic properties of the product sheet. As a result, it has been found that the magnetic properties are varied by the composition of the oxide-based inclusions existing in the steel sheet, particularly compositional ratio of CaO and compositional ratio of Al.sub.2O.sub.3.

(9) In order to change the composition of the oxide-based inclusions in the above steel of the above chemical composition, the inventors have melted steels having variously changed addition amounts of Al and Ca used as a deoxidizing agent, concretely various steels having a chemical composition comprising C: 0.0010-0.0030 mass %, Si: 3.2-3.4 mass %, Mn: 0.03 mass %, P: 0.09 mass %, S: 0.0010-0.0030 mass %, sol. Al: 0.0001-0.00030 mass %, N: 0.0010-0.0030 mass %, Sn: 0.03 mass % and Ca: 0.0010-0.0040 mass %, which are continuously cast into a steel slab, respectively. Moreover, the reason why each of C, Si, S and N has the above range is due to variation in the melting, which is not intended.

(10) Next, the steel slab is reheated to a temperature of 1100 C. and hot-rolled to obtain a hot rolled sheet of 2.0 mm in thickness, which is subjected to a hot band annealing at a soaking temperature of 1000*C, pickled, cold rolled to obtain a cold rolled sheet having a final thickness of 0.35 mm and thereafter subjected to finishing annealing at a temperature of 1000 C.

(11) From the thus obtained steel sheet after the finishing annealing are cut out Epstein test specimens in a rolling direction (L) and a direction perpendicular to the rolling direction (C), respectively, and a magnetic flux density B.sub.50 (magnetic flux density at a magnetization force of 5000 A/m) thereof is measured according to JIS C2552.

(12) Also, a section of the finishing annealed steel sheet in the direction perpendicular to the rolling direction is observed with a scanning electron microscope (SEM) to analyze a composition of oxide-based inclusions, from which are determined a compositional ratio of CaO defined by the following equation (1):
CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO)(1)
and a compositional ratio of Al.sub.2O.sub.3 defined by the following equation (2):
Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO)(2).

(13) Moreover, the compositional ratio of each of CaO and Al.sub.2O.sub.3 is an average value on 20 or more oxide-based inclusions.

(14) In FIG. 1 is shown a relation among a magnetic flux density B.sub.50 and a compositional ratio of CaO and a compositional ratio of Al.sub.2O.sub.3 in the oxide-based inclusions. As seen from this FIGURE, the magnetic flux density B.sub.50 is poor when the compositional ratio of CaO or CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO) is less than 0.4 and the compositional ratio of Al.sub.2O.sub.3 or Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO) is less than 0.3, whereas the magnetic flux density B.sub.50 is good in the finishing annealed steel sheets having CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO) of not less than 0.4 and/or Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO) of not less than 0.3.

(15) With respect to the hot rolled sheets for the finishing annealed steel sheets indicating the poor magnetic flux density B.sub.50, C-section is observed with the scanning electron microscope (SEM) to measure the compositional ratio of CaO and the compositional ratio of Al.sub.2O.sub.3 in the oxide-based inclusions, but the results are substantially the same as in the finishing annealed steel sheets.

(16) With respect to the finishing annealed steel sheets indicating the poor magnetic flux density B.sub.50, when the oxide-based inclusions at the section in the rolling direction are observed with an optical microscope, they have a form extending in the rolling direction.

(17) The inventors have the following thought on the above results.

(18) The oxide-based inclusions having a compositional ratio (CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO)) of CaO of less than 0.4 and a compositional ratio (Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO)) of Al.sub.2O.sub.3 of less than 0.3 have a tendency of extending in the rolling direction during the hot rolling because the melting point is low. The inclusions extended in the rolling direction are considered to block the grain growth in the hot band annealing and reduce the crystal grain size before the final cold rolling. In the finishing annealing, it is said that recrystallization nucleus with {111} orientation acting against the magnetic properties is caused from crystal grain boundary having a structure deformed by the cold rolling. However, since the grain size before the final cold rolling is reduced, the number of {111} orientations produced from the grain boundary is increased to promote the growth of {111} structure, and hence the magnetic flux density B.sub.50 is considered to become poor.

(19) The invention is developed based on the above new knowledge.

(20) The reason of limiting the chemical composition in the non-oriented electrical steel sheet according to the invention will be described below.

(21) C: Not More than 0.0050 Mass %

(22) C is an element increasing the iron loss. Particularly, when it exceeds 0.0050 mass %, the increase of the iron loss becomes remarkable, so that the content is limited to not more than 0.0050 mass %. Preferably, it is not more than 0.0030 mass %. Moreover, the lower limit is not particularly restricted because the content is preferable to become smaller.

(23) Si: More than 1.5 Mass % but not More than 5.0 Mass %

(24) Si is generally added as a deoxidizing agent for steel. In the electrical steel sheet, it is an element effective for increasing an electric resistance to reduce the iron loss. In the invention, Si is particularly a main element for increasing the electric resistance because another element for increasing the electric resistance such as Al, Mn or the like is not added, so that it is positively added in an amount exceeding 1.5 mass %. However, when Si exceeds 5.0 mass %, cracking is caused during the cold rolling to lower the productivity and decrease the magnetic flux density, so that the upper limit is 5.0 mass %. Preferably, it is within a range of 3.0-4.5 mass %.

(25) Mn: Not More than 0.10 Mass %

(26) Mn is desirable to become smaller for increasing the magnetic flux density. Also, Mn is a harmful element because when MnS is formed with S and precipitated, not only the movement of magnetic domain walls is blocked but also the grain growth is blocked to deteriorate the magnetic properties. From such a viewpoint, Mn is limited to not more than 0.10 mass %. Preferably, it is not more than 0.08 mass %. Moreover, the lower limit is not particularly restricted because the content is preferable to become smaller.

(27) P: More than 0.040 Mass % but not More than 0.2 Mass %

(28) P has an effect of increasing the magnetic flux density and is added in an amount exceeding 0.040 mass % in the invention. However, the excessive addition of P brings about the decrease of the rolling property, so that the upper limit is 0.2 mass %. Preferably, it is within a range of 0.05-0.1 mass %.

(29) S: Not More than 0.0050 Mass %

(30) S forms precipitates or inclusions to deteriorate the magnetic properties of a product, so that the content is preferable to become smaller. In the invention, Ca is added to suppress a bad influence of S, so that the upper limit is accepted up to 0.0050 mass %. Also, it is preferable to be not more than 0.0025 mass % so as not to deteriorate the magnetic properties. Moreover, the lower limit is not particularly restricted because the S content is preferable to become smaller.

(31) Sol. Al (Acid-Soluble Al): Not More than 0.0050 Mass %

(32) Al is generally added as a deoxidizing agent for steel like Si. In the electrical steel sheet, it is an element effective for increasing an electric resistance to reduce the iron loss. However, Al is also an element of blocking the grain growth to decrease the magnetic flux density by forming and precipitating a nitride. In the invention, therefore, sol. Al (acid-soluble Al) is restricted to not more than 0.0050 mass % for increasing the magnetic flux density. Preferably, it is not more than 0.0010 mass %. Moreover, the lower limit is not particularly restricted because the content is preferable to become smaller.

(33) N: Not More than 0.0040 Mass %

(34) N deteriorates the magnetic properties like C and is limited to not more than 0.0040 mass %. Preferably, it is not more than 0.0030 mass %. Moreover, the lower limit is not particularly restricted because the content is preferable to become smaller.

(35) Ca: 0.001-0.01 Mass %

(36) Ca has an effect of fixing S in steel to prevent the formation of liquidus FeS to thereby improve the hot rolling property. In the invention, the addition of Ca is essential because Mn content is lower than that of the usual non-oriented electrical steel sheet. In the steel according to the invention having a low Mn content, Ca has an effect of fixing S and promoting the grain growth to increase the magnetic flux density. In order to obtain these effects, the addition of not less than 0.001 mass % is necessary. On the other hand, when it is added in an amount exceeding 0.01 mass %, a sulfide or an oxide of Ca is increased to block the grain growth and decrease the magnetic flux density, so that the upper limit is necessary to be 0.01 mass %. Preferably, it is within a range of 0.002-0.004 mass %.

(37) In the non-oriented electrical steel sheet according to the invention, it is preferable to add Sn and Sb within the following range in addition to the above essential chemical composition.

(38) Sn, Sb: 0.01-0.1 Mass %

(39) Sn and Sb have an effect of improving the texture to enhance the magnetic properties. In order to obtain such an effect, even when they are added alone or in combination, each of them is preferable to be not less than 0.01 mass %. On the other hand, when they are added excessively, steel is embrittled to cause surface defects such as sheet breakage, scab and the like on the way of the production process, so that each of them is preferable to be not more than 0.1 mass % in case of either the single addition or the composite addition. Preferably, each of them is within a range of 0.02-0.05 mass %.

(40) In the non-oriented electrical steel sheet according to the invention, the remainder other than the above ingredients is Fe and inevitable impurities. However, other elements can be included within the scope not damaging the effect of the invention.

(41) The composition of the inclusions existing in the non-oriented electrical steel sheet according to the invention will be described below.

(42) In order that the non-oriented electrical steel sheet according to the invention has excellent magnetic properties, it is necessary that a compositional ratio (CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO)) of CaO is not less than 0.4 and a compositional ratio (Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO)) of Al.sub.2O.sub.3 is not less than 0.3 in the oxide-based inclusions existing in the product sheet (finishing annealed steel sheet) and the hot rolled steel sheet used as a raw material therefor. When the compositional ratio is outside the above range, the oxide-based inclusion is extended by rolling, which blocks the grain growth in the hot band annealing to deteriorate the magnetic properties. Preferably, the compositional ratio of CaO is not less than 0.5 and/or the compositional ratio of Al.sub.2O.sub.3 is not less than 0.4.

(43) Moreover, each of the compositional ratio of CaO and the compositional ratio of Al.sub.2O.sub.3 in the oxide-based inclusions existing in the steel sheet is an average value calculated from values obtained when the section of the steel sheet perpendicular to the rolling direction is observed with SEM (scanning electron microscope) to analyze chemical compositions of 20 or more oxide-based inclusions.

(44) Next, there will be described a method of controlling the composition of the inclusions existing in the non-oriented electrical steel sheet according to the invention to the above proper range.

(45) In order to control the composition of the inclusions, particularly the compositional ratio of CaO and the compositional ratio of Al.sub.2O.sub.3 to the above proper range, it is necessary to rationalize an addition amount of Si or Al as a deoxidizing agent in a secondary refining step, an addition amount of Ca, a deoxidizing time and so on.

(46) Concretely, an addition amount of Al.sub.2O.sub.3 as a deoxidizing agent is increased for enhancing the compositional ratio of Al.sub.2O.sub.3. However, as the addition amount of Al is increased, sol. Al is also increased, so that the addition amount of Al is increased to such a range that sol. Al is not more than 0.0050 mass %. On the other hand, in order to enhance the compositional ratio of CaO, Ca source such as CaSi or the like is added. Thus, the compositional ratio of the oxide-based inclusion exiting in steel can be controlled to the above range. Moreover, Al is a nitride forming element and Ca is a sulfide forming element, so that it is also important that the addition amounts of Al as a deoxidizing agent and the Ca source are adjusted so as to attain the above compositional ratios of CaO and Al.sub.2O.sub.3 in accordance with the N and S contents.

(47) There will be described the production method of the non-oriented electrical steel sheet according to the invention below.

(48) The non-oriented electrical steel sheet according to the invention can be produced with production facilities applied to the ordinary non-oriented electrical steel sheets and by the ordinary production process. In the production method of the non-oriented electrical steel sheet according to the invention, steel melted in a converter, an electric furnace or the like is first adjusted to a given chemical composition by secondary-refining with a degassing equipment or the like and then shaped into a raw steel material (slab) by a continuous casting method or an ingot making-blooming method.

(49) In the production method of the invention, it is most important to control the composition of the oxide-based inclusions existing in steel to the proper range as previously mentioned. That is, it is necessary to control a compositional ratio (CaO/(SiO.sub.2+Al.sub.2O.sub.3+CaO)) of CaO to not less than 0.4 and/or a compositional ratio (Al.sub.2O.sub.3/(SiO.sub.2+Al.sub.2O.sub.3+CaO)) of Al.sub.2O.sub.3 to not less than 0.3. This method is mentioned above.

(50) Thereafter, the thus obtained steel slab is subjected to hot rolling, hot band annealing, pickling, cold rolling, finishing annealing and further coating and baking of an insulating film to obtain a non-oriented electrical steel sheet (product sheet). In this case, production conditions of each step may be the same as in the production of the ordinary non-oriented electrical steel sheet, but are preferable to be the following ranges.

(51) At first, a temperature of reheating the slab (SRT) in the hot rolling is preferable to be a range of 1000-1200 C. When SRT exceeds 1200 C., not only the energy loss is uneconomically increased, but also the strength of the slab at a high temperature is decreased to easily cause production troubles such as slab sagging and the like. While when it is lower than 1000 C., it is difficult to perform the hot rolling and it becomes unfavorable.

(52) Further, the hot rolling may be carried out under ordinary conditions, but the thickness of the steel sheet after the hot rolling is preferably within a range of 1.5-2.8 mm in view of ensuring the productivity. More preferably, it is a range of 1.7-2.3 mm.

(53) The hot band annealing is preferable to be performed at a soaking temperature of 900-1150 C. When the soaking temperature is lower than 900 C., the rolled structure is retained, so that the effect of improving the magnetic properties is not obtained sufficiently. While when it exceeds 1150 C., the crystal grains are coarsened and hence cracking is easily caused in the cold rolling and becomes uneconomical.

(54) Next, the steel sheet after the hot band annealing is subjected to a single cold rolling or two or more cold rollings including an intermediate annealing therebetween to thereby obtain a cold rolled steel sheet having a final thickness. In this case, it is preferable to adopt a rolling performed by raising a sheet temperature to about 200 C. or a so-called warm rolling in order to enhance the magnetic flux density. Moreover, the thickness of the cold rolled sheet (final thickness) is not particularly limited, but is preferable to be a range of 0.10-0.50 mm. In order to obtain an effect of reducing the iron loss, it is more preferable to be a range of 0.10-0.30 mm.

(55) Subsequently, the steel sheet after the cold rolling (cold rolled sheet) is subjected to finishing annealing. In the finishing annealing, a soaking temperature is preferable to be a range of 700-1150 C. When the soaking temperature is lower than 700 C., the recrystallization is not promoted sufficiently and the magnetic properties are largely deteriorated and further the effect of correcting the sheet form in the continuous annealing is not obtained sufficiently. While when it exceeds 1150 C., the crystal grains are coarsened to increase the iron loss at a high frequency zone.

(56) In the steel sheet after the finishing annealing, it is preferable that an insulating film is applied to the steel sheet surface and baked for more reducing the iron loss. Moreover, it is preferable that the insulating film is a resin-containing organic coating when it is intended to ensure a good punchability or a semi-organic or an inorganic coating when a weldability is considered to be important.

Example 1

(57) Steels A-Q having different chemical compositions shown in Table 1 are melted and continuously cast into steel slabs. In the melting of the steel, Si is used as a deoxidizing agent, but Al is used as a deoxidizing agent in addition to Si in case of the steel B. Also, CaSi is used as a Ca source. The amount of the deoxidizing agent or CaSi is adjusted in accordance with the N or S content in steel.

(58) Next, the steel slab is reheated to a temperature of 1050-1130 C., hot-rolled to obtain a hot rolled steel sheet of 2.0 mm in thickness, which is subjected to a hot band annealing at a soaking temperature of 1000 C. in continuous annealing, cold-rolled to obtain a cold rolled steel sheet having a final thickness of 0.35 mm, subjected to finishing annealing at a soaking temperature of 1000 C. and coated with an insulating film to obtain a non-oriented electrical steel sheet (product sheet). In the steels E and Q shown in Table 1, cracking is caused during cold rolling, so that subsequent steps are stopped.

(59) TABLE-US-00001 TABLE 1 Steel Chemical composition (mass %) symbol C Si Mn P S sol. Al N Sn Sb Ca A 0.0017 3.36 0.024 0.08 0.0016 0.0008 0.0017 0.038 0.0032 B 0.0019 3.38 0.025 0.07 0.0016 0.0015 0.0016 0.039 0.0017 C 0.0018 3.37 0.024 0.08 0.0018 0.0005 0.0019 0.039 0.0018 D 0.0016 3.29 0.024 0.07 0.0017 0.0007 0.0018 0.028 0.0028 E 0.0017 5.15 0.032 0.07 0.0020 0.0009 0.0018 0.037 0.0032 F 0.0019 3.93 0.031 0.08 0.0018 0.0003 0.0021 0.028 0.0034 G 0.0014 1.85 0.029 0.08 0.0015 0.0015 0.0022 0.028 0.0036 H 0.0018 1.40 0.028 0.07 0.0019 0.0018 0.0016 0.029 0.0036 I 0.0021 3.21 0.057 0.12 0.0022 0.0008 0.0033 0.027 0.015 0.0035 J 0.0020 3.31 0.128 0.08 0.0022 0.0009 0.0020 0.031 0.025 0.0027 K 0.0018 3.28 0.046 0.08 0.0020 0.0001 0.0022 0.050 0.0028 L 0.0019 3.31 0.035 0.09 0.0024 0.0052 0.0029 0.044 0.0029 M 0.0021 3.27 0.036 0.14 0.0057 0.0015 0.0021 0.030 0.0027 N 0.0017 3.33 0.028 0.03 0.0017 0.0024 0.0017 0.037 0.0028 O 0.0019 3.30 0.022 0.05 0.0016 0.0011 0.0025 0.035 0.0031 P 0.0020 3.30 0.028 0.16 0.0018 0.0003 0.0019 0.036 0.0029 Q 0.0018 3.28 0.038 0.22 0.0022 0.0031 0.0018 0.035 0.0034 Compositional ratio of oxide-based inclusion Magnetic properties CaO/(SiO.sub.2 + Al.sub.2O.sub.3/(SiO.sub.2 + of product sheet Al.sub.2O.sub.3 + CaO) Al.sub.2O.sub.3 + CaO) Magnetic Hot Hot Iron flux rolled rolled loss density Steel steel Product steel Product W.sub.15/50 B.sub.50 symbol sheet sheet sheet sheet (W/kg) (T) Remarks A 0.5 0.5 0.1 0.1 1.98 1.712 Example B 0.3 0.3 0.4 0.4 2.01 1.711 Example C 0.3 0.3 0.2 0.2 2.15 1.693 Comparative Example D 0.4 0.5 0.2 0.1 2.02 1.710 Example E Cracking is caused during cold rolling Comparative Example F 0.5 0.4 0.1 0.1 1.88 1.701 Example G 0.5 0.5 0.3 0.2 2.45 1.749 Example H 0.6 0.7 0.3 0.3 2.61 1.758 Comparative Example I 0.5 0.5 0.2 0.2 1.96 1.715 Example J 0.4 0.4 0.2 0.2 2.12 1.694 Comparative Example K 0.5 0.5 0.1 0.1 1.97 1.715 Example L 0.5 0.5 0.5 0.5 2.19 1.691 Comparative Example M 0.4 0.4 0.4 0.4 2.21 1.690 Comparative Example N 0.5 0.5 0.3 0.3 2.16 1.694 Comparative Example O 0.5 0.5 0.2 0.2 2.08 1.702 Example P 0.5 0.5 0.1 0.1 1.94 1.719 Example Q Cracking is caused during cold rolling Comparative Example

(60) Then, sections of the hot rolled sheet and the steel sheet after the finishing annealing perpendicular to the rolling direction are observed by a scanning electron microscope (SEM) to analyze a chemical composition in 30 oxide-based inclusions and determine an average value thereof, from which a compositional ratio of CaO and a compositional ratio of Al.sub.2O.sub.3 are calculated.

(61) Also, Epstein test specimens are cut out from the product sheet in the rolling direction (L) and the direction perpendicular to the rolling direction (C), respectively, and the magnetic flux density B.sub.50 (magnetic flux density at a magnetization force of 5000 A/m) and iron loss W.sub.15/50 (iron loss in excitation at a magnetic flux density of 1.5 T and a frequency of 50 Hz) are measured according to JIS C2552.

(62) The above measured results are also shown in Table 1. As seen from these results, the steel sheets adapted to the invention can prevent the breakage in the rolling and maintain a high magnetic flux density that the magnetic flux density B.sub.50 is not less than 1.70 T, and have excellent magnetic properties.

Example 2

(63) Steels R-U having different chemical compositions shown in Table 2 are melted and continuously cast into steel slabs. In the melting of the steel. Si is used as a deoxidizing agent, but Al is used as a deoxidizing agent in addition to Si in case of the steel S. Also, CaSi is used as a Ca source. The amount of the deoxidizing agent or CaSi is adjusted in accordance with the N or S content in steel.

(64) Next, the steel slab is reheated to a temperature of 1050-1110 C., hot-rolled to obtain a hot rolled steel sheet of 1.6 mm in thickness, which is subjected to a hot band annealing at a soaking temperature of 1000 C. in continuous annealing, cold-rolled to obtain a cold rolled steel sheet having a final thickness of 0.15 mm, subjected to finishing annealing at a soaking temperature of 1000 C. and coated with an insulating film to obtain a non-oriented electrical steel sheet (product sheet).

(65) TABLE-US-00002 TABLE 2 Steel Chemical composition (mass %) symbol C Si Mn P S sol. Al N Sn Sb Ca R 0.0017 3.36 0.024 0.08 0.0016 0.0008 0.0017 0.038 0.0032 S 0.0019 3.38 0.025 0.07 0.0016 0.0015 0.0016 0.039 0.0017 T 0.0018 3.37 0.024 0.08 0.0018 0.0005 0.0019 0.039 0.0018 U 0.0017 3.37 0.025 0.01 0.0017 0.0006 0.0017 0.039 0.0001 Compositional ratio of oxide-based inclusion Magnetic properties CaO/(SiO.sub.2 + Al.sub.2O.sub.3/(SiO.sub.2 + of product sheet Al.sub.2O.sub.3 + CaO) Al.sub.2O.sub.3 + CaO) Magnetic Hot Hot Iron flux rolled rolled loss density Steel steel Product steel Product W.sub.10/800 B.sub.50 symbol sheet sheet sheet sheet (W/kg) (T) Remarks R 0.5 0.5 0.1 0.1 24.7 1.692 Example S 0.3 0.3 0.4 0.4 24.8 1.691 Example T 0.3 0.3 0.2 0.2 26.1 1.673 Comparative Example U 0.0 0.0 0.2 0.2 27.8 1.654 Comparative Example

(66) Then, sections of the hot rolled sheet and the steel sheet after the finishing annealing perpendicular to the rolling direction are observed by a scanning electron microscope (SEM) to analyze a chemical composition in 30 oxide-based inclusions and determine an average value thereof, from which a compositional ratio of CaO and a compositional ratio of Al.sub.2O.sub.3 are calculated.

(67) Also, Epstein test specimens are cut out from the product sheet in the rolling direction (L) and the direction perpendicular to the rolling direction (C), respectively, and the magnetic flux density B.sub.50 (magnetic flux density at a magnetization force of 5000 A/m) and iron loss W.sub.10/800 (iron loss in excitation at a magnetic flux density of 1.0 T and a frequency of 800 Hz) are measured according to JIS C2552.

(68) The above measured results are also shown in Table 2. As seen from these results, the steel sheets adapted to the invention can prevent the breakage in the rolling and reduce the iron loss W.sub.10/800 to not more than 25 W/kg while maintaining a high magnetic flux density that the magnetic flux density B.sub.50 is not less than 1.69 T, and have excellent magnetic properties at not only a commercial frequency but also a high frequency zone.

INDUSTRIAL APPLICABILITY

(69) According to the invention, material having a high magnetic flux density can be produced cheaply in a good productivity and have an effect of reducing a copper loss of a motor, so that they can be advantageously applied to an iron core for an induction motor having a tendency of increasing the copper loss as compared with the iron loss.