DESCRIPTION TITLE OF INVENTION: Fe-BASED METAL PLATE AND METHOD OF MANUFACTURING THE SAME TECHNICAL FIELD [0001] The present invention relates to a Fe-based metal plate used for a magnetic core or the like and a method of manufacturing the same. BACKGROUND ART [0002] Silicon steel plates have been conventionally-used for magnetic cores of electric motors, power generators, transformers, and the like. A silicon steel plate used for a magnetic core is required to be small in magnetic energy loss (core loss) in an alternating magnetic field and to be high in magnetic flux density in practical magnetic fields. To realize these, it is effective to increase electric resistance and to accumulate <100> axes being a • direction of easy magnetization of aFe, in a direction of a used magnetic field. Especially when {100} planes of aFe are highly accumulated in a surface (rolled surface) of a silicon steel plate, <100> axes are highly accumulated in the rolled surface, so that higher magnetic flux density can be obtained. Therefore, there have been proposed various techniques aiming at the higher accumulation of {100} planes in a surface of a silicon steel - 1 - plate. [0003] However, the conventional techniques have difficulty in realizing the stable high accumulation of [100] planes in a surface of a Fe-based metal plate such as a silicon steel plate. CITATION LIST PATENT LITERATURE [0004] Patent Literature 1: Japanese Laid-open Patent Publication No. 01-252727 Patent Literature 2: Japanese Laid-open Patent Publication No. 05-279740 Patent Literature 3: Japanese Laid-open Patent Publication No. 2007-51338 Patent Literature 4: Japanese Laid-open Patent Publication No. 2006-144116 Patent Literature 5: Japanese National Publication of International Patent Application No. 2010-513716 SUMMARY OF INVENTION TECHNICAL PROBLEM [0005] It is an object of the present invention to provide a Fe-based metal plate capable of having higher magnetic flux density and a method of manufacturing the same. SOLUTION TO PROBLEM [0006] (1) A method of manufacturing an Fe-based - 2 - metal plate including: forming a metal layer containing ferrite former on at least one surface of a base metal plate of an a-y transforming Fe or Fe alloy; next heating the base metal plate and the metal layer to an A3 point of the Fe or the Fe alloy so as to diffuse the ferrite former into the base metal plate and form an alloy region of a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less; and next heating the base metal plate to a temperature equal to or higher than the A3 point of the Fe or the Fe alloy so as to increase the accumulation degree of the {200} planes and decrease the accumulation degree of the {222} planes while maintaining the alloy region of the ferrite phase. [0007] (2) The method of manufacturing an Fe-based metal plate according to (1), including, after the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, cooling the base metal plate to a temperature lower than the A3 point of the Fe or the Fe alloy so as to transform an unalloyed region in the base metal plate from an austenitic phase to a ferrite phase, further increase the accumulation degree of the {200} planes and further decrease the accumulation degree of the {222} planes. [0008] (3) The method of manufacturing an Fe-based - 3 - metal plate according to (1) or (2), wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 30% or more and the accumulation degree of the {222} planes is decreased to 30% or less. [0009] (4) The method of manufacturing an Fe-based metal plate according to (1) or (2), wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 50% or more and the accumulation degree of the {222} planes is decreased to 15% or less. [0010] (5) The method of manufacturing an Fe-based metal plate according to any one of (1) to (4) , wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the ferrite former contained in the metal layer are all diffused into the base metal plate. [0011] (6) The method of manufacturing an Fe-based metal plate according to any one of (1) to (5) , wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn. [0012] (7) The method of manufacturing an Fe-based metal plate according to any one of (1) to (6), - 4 - wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, an area ratio of a ferrite single phase region to the metal plate in a cross section in a thickness direction is made to 1% or more. [0013] (8) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about and in which dislocation density is not less than 1 x lO''-^ m/m^ nor more than 1 x lO"''^ m/m^. [0014] (9) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in which rolling reduction ratio is not less than 97% nor more than 99.99%. [0015] (10) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about by shot blasting. [0016] (11) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in which rolling reduction ratio is not less than 50% nor more than 99.99% and shot blasting. [0017] (12) The method of manufacturing an Fe-based - 5 - metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a shear strain of 0.2 or more is brought about by cold rolling. [0018] (13) The method of manufacturing an Fe-based metal plate according to any one of (1) to (7), wherein as the base metal plate, used is one in which a shear strain of 0.1 or more is brought about by cold rolling and a working strain is brought about by shot blasting. [0019] (14) The method of manufacturing an Fe-based metal plate according to any one of (1) to (13), wherein a thickness of the base metal plate is not less than 10 i-im nor more than 5 mm. [0020] (15) A Fe-based metal plate, containing ferrite former, wherein, in a surface, an accumulation degree of {200} planes in a ferrite phase is 30% or more and an accumulation degree of {222} planes in the ferrite phase is 30% or less. [0021] (16) The Fe-based metal plate according to (15), being formed by diffusion of the ferrite former from a surface to an inner part of an a-y transforming Fe or Fe alloy plate. [0022] (17) The Fe-based metal plate according to (15) or (16), including, on the surface, a metal layer containing the ferrite former. [0023] (18) The Fe-based metal plate according to any one of (15) to (17), wherein the accumulation degree of the {200} planes is 50% or more and the - 6 - accumulation degree of the {222} planes is 15% or less . [0024] (19) The Fe-based metal plate according to any one of (15) to (18), wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn. [0025] (20) The Fe-based metal plate according to any one of (15) to (19), including a 1% ferrite single phase region or more in terms of an area ratio in a thicknesswise cross section of the metal plate. [0026] The accumulation degree of the {200} planes in the ferrite phase is expressed by an expression (1) and the accumulation degree of the {222} planes in the ferrite phase is expressed by an expression (2) . accumulation degree of {200} planes = [ {i (200)/I (200) }/S{i(hkl) /I (hkl) }] x lOO ... (1) accumulation degree of {222} planes = [ {i (222)/I (222) }/S{i(hkl)/I (hkl) }] x lOO ... (2) Here, i(hkl) is actually measured integrated intensity of {hkl} planes in the surface of the Fe-based metal plate or the base metal plate, and I(hkl) is theoretical integrated intensity of {hkl} planes in a sample having random orientation. As the (hkl) planes, used are, for examples, 11 kinds of {110}, {200}, {211}, {310}, {222}, {321}, {411}, {420}, {332}, {521}, and {442} planes. - 7 - ADVANTAGEOUS EFFECTS OF INVENTION [0027] According to the present invention, it is possible to obtain a Fe-based metal plate in which an accumulation degree of {200} planes in a ferrite phase is high and an accumulation degree of {222} planes in the ferrite phase is low, and to improve magnetic flux density. BRIEF DESCRIPTION OF DRAWINGS [0028] [Fig. lA] Fig. lA is a cross-sectional view showing a basic principle of the present invention. [Fig. IB] Fig. IB, which continues from Fig. lA, is a cross-sectional view showing the basic principle of the present invention. [Fig. IC] Fig. IC, which continues from Fig. IB, is a cross-sectional view showing the basic principle of the present invention. [Fig. ID] Fig. ID, which continues from Fig. IC, is a cross-sectional view showing the basic principle of the present invention. [Fig. IE] Fig. IE, which continues from Fig. ID, is a cross-sectional view showing the basic principle of the present invention. [Fig. 2A] Fig. 2A is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to a first embodiment. [Fig. 2B] Fig. 2B, which continues from Fig. 2A, is a cross-sectional view showing the method of manufacturing the Fe-based metal plate. - 8 - [Fig. 2C] Fig. 2C, which continues from Fig. 2B, is a cross-sectional view showing the method of manufacturing the Fe-based metal plate. [Fig. 2D] Fig. 2D, which continues from Fig. 2C, is a cross-sectional view showing the method of manufacturing the Fe-based metal plate. [Fig. 3] Fig. 3 is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to a second embodiment. [Fig. 4] Fig. 4 is a cross-sectional view showing a method of manufacturing a Fe-based metal plate according to a third embodiment. DESCRIPTION OF EMBODIMENTS [0029] (Basic Principle of Present Invention) First, a basic principle of the present invention will be described. Fig. lA to Fig. IE are cross-sectional views showing the basic principle of the present invention. [0030] In the present invention, for example, as illustrated in Fig. lA, a metal layer 2 containing ferrite former is formed on at least one surface of a base metal plate 1 composed of an a-y transforming Fe-based metal (Fe or Fe alloy). As the base metal plate 1, for example, pure iron plate cold-rolled with a very high rolling reduction ratio of about 99.8% is used. Further, as the metal layer 2, an Al layer is formed, for example. [0031] Next, the base metal plate 1 and the metal - 9 - layer 2 are heated to the A3 point of the material (pure iron) of the base metal plate 1. During the heating, as illustrated in Fig. IB, Al being the ferrite former in the metal layer 2 is diffused into the base metal plate 1, so that an alloy region lb in a ferrite phase (a phase) is formed. The remainder of the base metal plate 1 is an unalloyed region la in the a phase until an instant immediately before the A3 point is reached. In accordance with the heating, recrystallization occurs in the alloy region lb and the unalloyed region la. Further, since a large strain has been generated due to the cold rolling, planes parallel to a surface of the base metal plate 1 (rolled surface), of grains generated by the recrystaliization are likely to be oriented in {100}. Therefore, many grains whose planes parallel to the rolled surface are oriented in {100} are generated both in the alloy region lb and the unalloyed region la. Here, important points of the present invention are that, by the instant before the temperature reaches the A3 point,a-phase grains oriented in {100} are contained in the alloy region lb due to the diffusion of Al being the ferrite former, and that the alloy region lb has the a. single phase alloy composition. [0032] Thereafter, the base metal plate 1 and the metal layer 2 are further heated to a temperature equal to or higher than the A3 point of the pure iron. As a result, as illustrated in Fig. IC, the - 10 - unalloyed region la composed of the pure iron is Y~ transformed to become an austenitic phase (y phase), while the alloy region lb containing Al being the ferrite former is maintained in the a phase. Even at the temperature equal to or higher than the A3 point, the a-phase grains oriented in {100}, which are formed at lower than the A3 point, do not undergo the y-transformation and their crystal orientation is maintained. Further, in the alloy region lb, grains 3 whose planes parallel to the rolled surface are oriented in {100} predominantly grow. Along with the growth of the {100} grains, grains oriented in other directions vanish. For example, grains whose planes parallel to the rolled surface are oriented in {111} decrease. Therefore, in the alloy region lb, the accumulation degree of {200} planes in the a phase increases and the accumulation degree of {222} planes in the a phase decreases. [0033] Then, when the base metal plate 1 and the metal layer 2 are kept at the temperature equal to or higher than the A3 point of the pure iron, Al in the metal layer 2 further diffuses into the base metal plate 1, and as illustrated in Fig. ID, the alloy region lb in the a phase expands. That is, in accordance with the diffusion of Al being the ferrite former, part of the unalloyed region la in the y phase changes to the alloy region lb in the a phase. At the time of this change, since the alloy region lb being a region adjacent to a metal layer 2 side of - 11 - the region where the change occurs has already been oriented in {100}, the region where the change occurs takes over the crystal orientation of the alloy region lb to be oriented in {100}. As a result, the grains 3 whose planes parallel to the rolled surface are oriented in {100} further grow. Then, along with the growth of the grains 3, the accumulation degree of the {200} planes in the a phase further increases and the accumulation degree of the {222} planes in the a phase further decreases. [0034] Subsequently, the base metal plate 1 is cooled to a temperature lower than the A3 point of the pure iron. As a result, as illustrated in Fig. IE, the unalloyed region la composed of the pure iron is a-trans formed to the a phase. At the time of the phase transformation as well, since the alloy region lb being the region adjacent to the metal layer 2 side of the region where the phase transformation occurs has already been oriented in {100}, the region where the phase transformation occurs takes over the crystal orientation of the alloy region lb to be oriented in {100}. As a result, the grains 3 whose planes parallel to the rolled surface are oriented in [100} further grow. Then, along with the growth of the grains 3, the accumulation degree of the {200} planes in the a phase further increases and the accumulation degree of the {222} planes in the a phase further decreases. That is, a high accumulation degree of the {200} planes in the a - 12 - phase is obtained also in the unalloyed region la. [0035] Incidentally, when the metal layer 2 is thick and the keeping time of the temperature equal to or higher than the A3 point is long, Al sufficiently diffuses and the unalloyed region la sometimes disappears before the temperature of the base metal plate 1 reaches lower than the A3 point at the time of the cooling. In this case, the phase transformation of the unalloyed region la does not occur, and since the whole region has become the alloy region lb, the state at the start of the cooling is maintained. [0036] Therefore, in the Fe-based metal plate (Fe or Fe alloy plate) manufactured through these processes, the accumulation degree of the {200} planes in the a phase is extremely high and the accumulation degree of the {222} planes in the a phase is extremely low. Therefore, high magnetic flux density is obtained. [0037] Here, conditions in the present invention will be described. [0038] "Base Metal Plate" As a material of the base metal plate, an oc-y transforming Fe-based metal (Fe or Fe alloy) is used. The Fe-based metal contains, for example, 70 mass% Fe or more. Further, the a-y transformation series is, for example, a component series which has the A3 point within a range of about 600°C to 1000°C, and which has an a phase as its main phase at lower than the A3 point and has a y phase as its main phase at - 13 - the A3 point or higher. Here, the main phase refers to a phase whose volume ratio is over 50%. The use of the a-Y transforming Fe-based metal makes it possible to form a region having an a single phase composition in accordance with the diffusion and alloying of a ferrite former. Examples of the a-y transforming Fe-based metal may be pure iron, low-carbon steel, and the like. For example, usable is pure iron whose C content is 1 mass ppm to 0.2 mass%, with the balance being Fe and inevitable impurities. Also usable is silicon steel composed of an oc-y transforming component whose basic components are C with a 0.1 mass% content or less and Si with a 0.1 mass% to 2.5 mass% content. Further, any of these to which various kinds of elements are added may also be used. Examples of the various elements are Mn, Ni, Cr, Al, Mo, W, V, Ti, Nb, B, Cu, Co, Zr, Y, Hf, La, Ce, N, 0, P, S, and so on. However, it is preferable that Mn and Ni are not contained because they may involve a risk of lowering magnetic flux density. [0039] As the base metal plate, one in which a strain is brought about is used, for example. This is intended to generate many grains whose planes parallel to the rolled surface are oriented in {100}, at the time of the recrystaliization of the base metal plate, thereby improving the accumulation degree of the {200} planes in the a phase. For example, it is preferable to bring about a working strain with which dislocation density becomes not - 14 - less than 1 x 10^^ m/in'^ nor more than 1 x 10^^ m/ia^. A method for generating such a strain is not particularly limited, but, for example, it is preferable to apply cold rolling with a high rolling reduction ratio, especially with a rolling reduction ratio of not less than 97% nor more than 99.99%. Alternatively, a shear strain of 0.2 or more may be generated by cold rolling. It is possible to generate the shear strain by, for example, rotating upper and lower reduction rolls at different speeds at the time of the cold rolling. In this case, the larger a difference in the rotation speed between the upper and lower reduction rolls, the larger the shear strain. The shear strain may be calculated from diameters of the reduction rolls and a difference in rotation speed therebetween. [0040] The strain need not exist all along the thickness direction of the base metal plate, and the strain only needs to exist in a portion where the formation of the alloyed region starts, that is, in a surface layer portion of the base metal plate. Therefore, the working strain may be brought about by shot blasting, or the generation of the working strain or the generation of the shear strain by the cold rolling may be combined with the generation of the working strain by the shot blasting. When the cold rolling and the shot blasting are combined, a rolling reduction ratio of the cold rolling may be not less than 50% nor more than 99.99%. When the - 15 - generation of the shear strain and the shot blasting are combined, the shear strain may be 0.1 or more. When the working strain is brought about by the shot blasting, it is possible to make the orientation of the {100} planes of the grains uniform in planes parallel to the surface of the Fe-based metal plate. [0041] As the base metal plate, one in which a texture oriented in {100} is formed in the surface layer portion in advance may be used, for example. In this case as well, in the alloy region, it is possible to increase the accumulation degree of the {200} planes in the a phase and decrease the accumulation degree of the {222} planes in the a phase. It is possible to obtain such a base metal plate by, for example, subjecting a metal plate including a large strain to recrystallization annealing. [0042] Though details will be described later, a base metal plate may be used in which an a-phase alloy region where the accumulation degree of the {200} planes in the a phase is 25% or more and the accumulation degree of the {222} planes in the a phase is 40% or less is formed at the time of the heating to the A3 point. [0043] A thickness of the base metal plate is preferably not less than 10 jjm nor more than 5 mm, for example. As will be described later, a thickness of the Fe-based metal plate is preferably more than 10 lam and 6 mm or less. Considering that the metal - 16 - layer is formed, when the thickness of the base metal plate is not less than 10 ym nor more than 5 mm, the thickness of the Fe-based metal plate may be easily more than 10 \im and 6 mm or less. [0044] "Ferrite former and Metal Layer" As the ferrite former, Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ta, Ti, V, W, Zn, or the like is preferably used. The use of any of these elements facilitates forming the region having the a single phase composition and makes it possible to efficiently enhance the accumulation degree of the {200} planes in the a phase. [0045] A method of forming the metal layer containing the ferrite former is not particularly limited, and examples thereof may be plating methods such as a hot dipping method and an electrolytic plating method, dry process methods such as a PVD (physical vapor deposition) method and a CVD ■ (chemical vapor deposition) method, a rolling clad method, powder coating, and so on. Among them, the plating method and the rolling clad method are preferable especially when the method is industrially implemented. This is because they may easily and efficiently form the metal layer. [0046] A thickness of the metal layer is preferably not less than 0.05 ym nor more than 1000 \im. When the thickness of the metal layer is less than 0.05 lam, it may be difficult to sufficiently form the alloy region and it is not sometimes possible to - 17 - obtain the sufficient accumulation degree of the {200} planes in the a phase. Further, when the thickness of the metal layer is over 1000 pm, the metal layer sometimes remains thickly after the cooling to lower than the A3 point and a high magnetic property cannot be sometimes obtained. [0047] "Ratio of Alloying of Metal Layer" In the metal layer, a ratio of its portion alloyed with the base metal plate is preferably 10% or more in the thickness direction. When the ratio is less than 10%, it may be difficult to sufficiently form the alloy region and it is not sometimes possible to obtain the sufficient accumulation degree of-the {200} planes in the a. phase. Incidentally, the ratio (alloying ratio) may be expressed by an expression (3), where SO is an area of the metal layer before the heating in a cross section perpendicular to the surface of the base metal plate and S is « 5 5 5 5 5 5 5 I 11 =22 2= = = = = = --, „„„.„ = = = = = = |_^i_____i i i i i = I 3 5 3 3 3 55533 aaaaa >>>>> & 6 6 & 6 5<^-?<-< II §ssss§iissgii§§§§§?????s§§ii§§ii§i§§i ie"-? =2 % == == =o =o =o % % =o =o % % % % % % % % % \ == V =2 =2 % % % % % > % % % \ % % |i_ |p,„..„„„„„,,,,„„„,,.„,,„ i^T I lllllllllliililllllllilliiiillllilill o <<<<< N 0.0002 1.4 0.005 0.1 0.0004 0.005 <0.0004 0.003 1010 O 0.0002 1.1 0.1 0.3 0.0004 0.005 <0.0004 0.003 1005 P 0.0002 1.3 0.2 0.2 0.0004 0.005 <0.0004 0.003 1010 Q 0.0002 0.9 0.15 0.6 0.0004 0.004 <0.0004 0.003 1020 R 0.0003 1.0 0.1S 0.4 0.0003 0.004 <0.0004 0.003 1010 S 0.0002 1.5 0.08 0.5 0.0003 0.004 <0.0004 0.003 1080 T 0.0003 0.005 0.12 0.6 0.0004 0.004 <0.0004 0.003 1020 U 0.0003 0.6 0.1 0.65 0.0004 0.004 <0.0004 0.003 Cr.2% 1000 V 0.0003 0.8 0.1 0.S 0.0004 0.004 <0.0004 0.003 Mo:1!( 1000 W 0.0003 0.2 O.OS 0.7 0.0004 0.004 <0.0004 0.003 V:0.5X 1010 [0126] The cold rolling was performed under the following conditions. In the conditions No. 4-1 to 4-7, the hot-rolled plates with a 2.0 mm thickness were pickled to remove scales, and thereafter were rolled to a 0.1 mm thickness. A rolling reduction ratio at this time was 95%. In the conditions No. 4-8 to 4-14, the hot-rolled plates with a 4.0 mm thickness were pickled to remove scales, and thereafter were rolled to a 0.1 mm thickness. A rolling reduction ratio at this time was 97.5%. In the conditions No. 4-15 to 4-21,- the hot-rolled steel plates with a 2.0 mm thickness were subjected- to shot blasting as hard surface machining on both surfaces, - 65 - and thereafter were rolled to a 0.1 mm thickness. A rolling reduction ratio at this time was 95%. In the shot blasting, iron beads with a 1 mm to 3 mm diameter were made to continuously collide with the both surfaces of the base metal plates for 10 seconds each. In the conditions No. 4-22 to 4-28, the hot-rolled plates with a 5.0 mm thickness were pickled to remove scales and thereafter were rolled to a 0.25 mm thickness. A rolling reduction ratio at this time was 95%. In the conditions No. 4-29 to 4-35, the hot-rolled plates with a 10.0 mm thickness were pickled to remove scales, and thereafter were rolled to a 0.2 5 mm thickness. A rolling reduction ratio at this time was 97.5%. In the conditions No. 4-36 to 4-42, the hot-rolled plates with a 5.0 mm thickness were subjected to shot blasting as hard surface machining on both surfaces and thereafter were cold-rolled to a 0.25 mm thickness. A rolling reduction ratio at this time was 95%. In this shot blasting, iron beads with a 1 mm to 3 mm diameter were made to continuously collide with the both surfaces of the base metal plates for ten seconds each. [0127] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 pm from the surface, dislocation density in this region - 66 - was measured. Average values of the obtained dislocation densities are listed in Table 12. [0128] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0129] Thereafter, Al layers as the metal layers were formed on the front surface and the rear surface of each of the base metal plates by a vapor deposition method, except in the conditions No. 4-1, No. 4-8, No. 4-15, No. 4-22, No. 4-29, and No. 4-36. Thickness of each of the Al layers (total thiclcness on the both surfaces) is listed in Table 12. [0130] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 12. - 67 - [0131] [Table 12] - 68 - Ss2s s =S2S22 5 S----" 5 ^-"^"S = =».»»- s ;5S55;i = 2SSS2- pi |islg2 gsssss 2 SS2SSS 2 sssspB 2 ssssss = 3SSSSS = =sasaa iPi || 8 IXSSSS S XSS33S S SSSSSSK SSSSSS S SSSSSS S S8SSSS |P 8 818888 8 8888|8 8 88SS88 | 888888 S 88Si|8 S 8gg8S8 |22 2 S222S2 2 S5 55:;~ 2 5"S522 2 =»<.--« 2 5 5;5;;:55 2 SSSSSS m jls^gC 8SS5SS 2 SSSSSS 2 SKSSSS 2 SSSSSS 2 JSSSSS 2 SSSSSS Ifi " p3 ~ -.-.SSI . .„-S5SS .„„.8Si ..o.gSS „ .o.sSS . «?§ |ig i liiiii I iiiiiiliiiiii iiiiiiiIiiiiiiiiiiiii is^g t «: = :-= : 333SSS = 3323S3 s =222 = 2 = 293333 S 3S233S l!i_ _ _ - _ _ iL ___ ^ ||e i iiiiii iiiiiii i llliil iiiiiii iiiiiii iiiiiii ^ . P ":::::-:::::r::::::-:::;:r;:::;r:::::: ^^_L_ I I i i I I ^ S <<<<<5 <5<<3< <<<55< <<<<<< ;n/R WlO/lk No. ^T PHASE (200} PLANE (2221 PLANE (T) (T) "'"'"* (W/kg) ^2 2i iS^ 22 °°"'^'^[!*™^ 4-1 0 0 13 13 1.60 2.05 0.78 92 EXAMPLE __^____^_^__ „________ ____^__^_ ^^___—_^™____ ^^—.^^__^^__.—_ ^__-^ ^^^__- —^_-—. 4-2 9 OJ 30 n 1.74 2.05 0.85 65 EXAMPLE 4-3 82 1^5 31 10 1J4_ 2.05 0.85 57 OF 4-4 95 82 30 10 ]Ji_ 2.05 0.85 44 PRESENT 4-5 100 35 30 10 124_ 2.05 0.85 37 INVENTION 4-6 10O 73 30 10 L74_ 2.05 0.85 43 4-7 100 87 30 10 1.74 2.05 0.85 58 °°.^JVJ^T!^^ 4-8 0 0 13 13 1.60 2.05 0.78 90 EXAMPLE 4-9 10 03 45 5^2 1.78 2.05 0.87 63 r.>,.i.n, ,= 4-10 64 2.6 53 2.7 1.85 2.05 0.90 57 EXAMPLE _—_^—^ ' ' ——_—^-_—_ OF 4-11 94 7J 53 2J 1£7_ 2.05 0.91 42 PRESENT 4-12 100 42 53 TT t85_ 2.05 0.90 33 INVENTION 4-13 100 71 53 2^7 1^ 2.05 0.90 38 4-14 100 95 53 2.7 1.87 2.05 0.91 53 ^°EXmP\S^ 4-15 0 0 13 13 1.62 2.05 0.79 92 4-16 8 0.2 62 2.1 ~ 1.89 "loT 0.92 62 cvAUDic 4-17 67 1.2 75 1.3 1.95 2.05 0.95 48 EXAMPLE OF 4-18 89 5^9 75 1L4 1.93 2.05 0.94 41 PRESENT 4-19 100 37 75 L3 L95_ 2.05 0.95 28 INVENTION 4-20 100 72 76 ]A 1£7_ 2.05 0.96 33 4-21 100 87 75 U 1.95 2.05 0.95 48 °°"'''^[^™^ 4-22 0 0 13 13 1.60 2.05 0.78 98 EXAMPLE 4-23 7 05 30 1J 1.74 2.05 085 63 EXAMPLE 4-24 57 h2 32 9 ]JA_ 2.05 0.85 56 OF 4-25 87 6J 32 9 U4_ 2.05 0.85 45 PRESENT 4-26 100 45 32 9 U4_ 2.05 0.85 37 INVENTION 4-27 100 72 32 9 U4_ 2.05 0.85 42 4-28 100 92 32 9 1.74 2.05 0.85 57 °°^"v1u'^^ 4-29 0 0 13 13 1.60 2.05 0.78 96 EXAMPLE _^_^___^ , 4-30 6 03 44 4^8 1.80 2.05 0.88 65 EXAMPLE 4-31 54 1J 56 2J 1.87 2.05 0.91 52 OF 4-32 78 6J 56 2J 1.85 2.05 090 41 PRESENT 4-33 100 M 56 22 1£7_ 2.05 091 32 INVENTION 4-34 100 71 56 2.1 1.85 205 0.90 38 4-35 100 91 56 2.2 1.87 2.05 0.91 54 °°EXAMPLE^ 4-36 0 0 13 13 1.62 2.05 0.79 101 4-37 8 02 61 2J 1.91 2.05" 0.93 61 EXAMPLE 4-38 70 2^3 82 08 1.95 2.05 0.95 46 OF 4-39 91 7J 82 OA 1^ 2.05 0.95 40 PRESENT 4-40 100 41 82 08 1.97 2.05 0.96 26 INVENTION -^—^—— ^—^—— ^——— 4-41 100 76 82 08 1.95 2.05 0.95 32 4-42 100 100 82 08 1.97 2.05 096 48 [0135] As listed in Table 12, in examples of the present invention (conditions No. 4-2 to No. 4-7, No. 4-9 to No. 4-14, No. 4-16 to No. 4-21, No. 4-23 to No. 4-28, No. 4-30 to No. 4-35, No. 4-37 to No. 4- - 71 - 42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the haat treatment. Further, as listed in Table 13, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 13, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/BS was 0.85 or more. [0136] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0137] (Fifth Experiment) In a fifth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. - 72 - 5-1 to condition No. 5-42) were studied. [0138] Base metal plates (silicon steel plates) used in the fifth experiment contained components of the composition 0 listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the fifth experiment transformed to a Y single phase was 1005°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 5-1 to the condition No. 5-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0139] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 pm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 14. [0140] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation - 73 - degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0141] Thereafter, Si layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a vapor deposition method, except in the conditions No. 5-1, No. 5-8, No. 5-15, No. 5-22, No. 5-29, and No. 5-36. Thickness of each of the Si layers (total thickness on the both surfaces) is listed in Table 14. [0142] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a. phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 14. [0143] [Table 14] - 74 - 11°; I I I I I I I I TT pi 53gEg2 ssaass 2 ssssss 2 ssssss 2 ssssss 2 ssssss 2 ssssss If II s ssssss s ssssss s sxssss a ssssss s sssgss s ssssss III i laasaa § laaasa § lasaaa I Sgaaaa | §asssg § gosaas gtg 2 a-...- 2 S55555 2 s;:::;:; 2 ssssss 2 -SSSSS 2 5S3S3S §1 SEg 5 SgSSSH 2 ?SiSS2S 2 SSSSSS 2 g5S55S 2 SSSSSS 2 SSSSSS ,Ji. ijg iiiiiiiiiiiiii iiiiiii i|ii!ii III!!!! ! Hill! Is^gs 222222 2 5;;;;5 2 S33333 s :;-:♦- 2 SSSSSS = 222252 pi flf ; fig iliiiii i iiiiii i iiiiii iiiilii I iiiiii i iiiiii ill a aaasaa a aassaa a aaaaaa a aaaaaa a aaaaaa 3 aaaaaa ^ i| 222S22 22SSS2 2SSS2° SSSSSS SaSSSS SSSSSS ^41 i ______ i i i I i 3 s inunmuu nSiSncau nnuuiaw a m a a tX S S S a a i« 9 a a M K a a II S 8S8S88 S SSSSSS § SSSS88 S SggSgS S SSgSSS S ggSSSS h-1 % =2=2=2=2=2% =2 =2'2 =2 =2=2 =2 =2 =2=2=2=2=2=2 =2 =2=2=2=2=2=2 =2 =2^=2=2=2=2 =2 =2=2=2=2=2=0 ogg X X X H X X X X xxxxxx X xxxxxx X xxxxxx X xxxxxx X xxxxxx I i|« S SSSSSS ^ SS^ilS S SSSSSS S SSSSSS i SSSSSS - SSSSSS o o 000000 o 000000 o 000000 o 000000 o 000000 o 000000 [0144] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each Fe-based metal plate were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and. the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the Si content was 1.9 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 15. [0145] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/lk (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 15. [0146] [Table 15] - 76 - TABLE 15 I I Ai nYiwr I •'*^° °^ I ACCUMULATION 1 ACCUMULATION I I I I CONOmON o"-Ii or SINGLE DEGREE OF DEGREE OF B50 Bs WlO/lk No. fl PHASE 1200) PLANE {222} PLANE (T) (D "™'"* (W/kg) '•_ 22 00 22 °°"f*''^ll^ 5-1 0 0 13 13 1.61 2.07 0.78 93 EXAMPLE ^.^_^—...^ ^^__.^^^—.^^ —.^^—.^^-.^-. 5-2 8 02 31 12 1.76 2.07 0.85 64 CVA.101 c 5-3 67 2.1 32 9 1.78 2.07 0.86 59 EXAMPLE ^——— ■^—^— ^^-—^^— ———^^^— OF 5-4 89 7^6 32 9 1.78 2.07 0.86 45 PRESENT 5-5 100 40 32 9 U8_ 2.07 0.86 38 INVENTION g_g 100 71 32 9 U8_ 2.07 0.86 42 5-7 100 95 32 9 1.78 2.07 0.86 59 '^°^J'A1!^Y*'^ 5-8 0 0 13 13 1.61 2.07 0.78 91 5-9 10 OJ 43 57 1.80 2.07 0.87 62 cv».inic 5-10 51 1.2 55 2.1 1.88 2.07 0.91 53 EXAMPLE ——^— OF 5-11 82 5^9 55 2J 1^ 2.07 0.91 41 PRESENT 5-12 100 38 55 2J L88_ 2.07 0.91 32 INVENTION 5-)3 100 72 55 2J L88_ 2.07 0.91 35 5-14 100 89 55 2.1 1.88 2.07 0.91 53 °°E)WMPLE^ 5-15 0 0 13 13 1.64 2.07 0.79 94 5-16 8 0.2 " 58 2.4 ~ 1.90 TOT" 0.92 61 EXAMPLE 5-17 72 2J 78 LI 1^ 2.07 0.96 47 OF 5-18 87 S£ 78 U L99_ 2.07 096 40 PRESENT 5-19 100 42 78 U L99_ 2.07 096 29 INVENTION 5-20 100 62 78 U L99_ 2.07 0.96 32 5-21 100 90 78 1.1 1.99 2.07 0.96 48 TJSIS^IT^ 5-22 0 0 13 13 _1^ 2.07 0.78 102 5-23 7 05 30 12 1.76 2.07 085 61 EXAMPLE 5-24 62 L6 31 10 L78_ 2.07 0.86 59 OF 5-25 86 7J 31 10 1.78 2.07 086 43 PRESENT 5-26 100 32 31 10 1.78 2.07 0.86 36 INVENTION 5-27 100 63 31 10 U8_ 2.07 0.86 41 5-28 100 100 31 10 1.78 2.07 0.86 57 """^r^lT^ 5-29 0 0 U 13 1.61 2.07 0.78 97 5-30 6 03 42 ~ 5 TsT 2.07 ~ 088 62 gj^^UPLg 5-31 46 LJ 58 L9 L86_ 207 O90 53 OF 5-32 82 8^3 58 L9 1.86 2.07 0.90 41 PRESENT 5-33 100 43 58 15 L86_ 2.07 O90 33 "^^^'^^'°'^ 5-34 100 72 58 L9 1.86 2.07 0.90 37 5-35 100 98 58 1.9 1.86 2.07 0.90 54 ''"ST" S-3« ° ° If 13 1.64 2.07 0.79 98 5-37 8 02 62 2J 1.93 2.07 0.93 ~ 64 gj^^l^jpLE 5-38 69 37 87 03 1.99 2.07 0.96 46 OF 5-39 89 BA 87 03 1.99 2.07 0.96 40 PRESENT 5-40 100 45 87 03 1.99 2.07 096 27 INVENTION 5-41 100 68 87 03 ]S9_ 2.07 096 34 5-42 100 92 87 0.3 1.99 2.07 0.96 46 [0147] As listed in Table 14, in examples of the present invention (conditions No. 5-2 to No. 5-7, No. 5-9 to No. 5-14, No. 5-16 to No. 5-21, No. 5-23 to No. 5-28, No. 5-30 to No. 5-35, No. 5-37 to No. 5- - 77 - T2) , the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the ' respective stages of the heat treatment. Further, as listed in Table 15, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 15, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more. [0148] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0149] (Sixth Experiment) In a sixth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. - 78 - 6-1 to condition No. 6-42) were studied. [0150] Base metal plates (silicon steel plates) used in the sixth experiment contained components of the composition P listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the sixth experiment transformed to a Y single phase was 1010°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 6-1 to the condition No. 6-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0151] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 \im from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 16. [0152] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation - 79 - degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0153] Thereafter, Sn layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by an electroplating method, except in the conditions No. 6-1, No. 6-8, No. 6-15, No. 6-22, No. 6-29, and No. 6-36. Thickness of each of the Sn layers (total thickness on the both surfaces) is listed in Table 16. [0154] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 16. [0155] [Table 16] - 80 - |2s 2 =.---- 2 32 = 2;: s 35SSSS = s---"- = 5323"-13 2 533SSS n |=S^s= gsssas 5 5SSSSS = ssssss s ssssss = ssssss = BSSSS? fPi || 8 SSSSSS s SSSSSS g ssssss s ssssss s ssssss a ssssss Is^R s =--.-» S 325522 2 HSSSSS 5 s----- S 5333153 2 533333 P_ lil^g 2 sassas = ssssss 2 ssssss 2 ssssss 2 ssssss 2 sssss? ifi- I jg I 1111 I I I 111 I II IIII III II III 11 IIIII11 g III i II igSg 2 iiii?: 2 «„«„„«, 2 33 233 S 2 :if-s = ? 2 j^vviv 2 3332S3 i!i ii_ _ j^ jig I i 111 i i 11 i i i i i i 11 i i I i i i i 111 i i i i i i i i 11 i i i 1 i "^ ||S S 222S22 S 2222SS 2 SSS22S S 2S2SS° 2 2S2S2° 2 S2222S 5 |l 32S3S3 3S23SS 323323 «- = .-- _--„.. .. ix i i — i — i i i ll §§§88888S|88888888888§Sg|g§§agggggg§8SS8Sa i|-| =o ===0=0=0=0% =g =S=2=2%%=o % =0=0=0=0=0=0 % =0=0=0=0=0=0 =g =0=0=0=2=0=2 =0 =0=0=0=0=0=0 OfiJ X XXXKXX X XXXXXX X XXXXXX X XXXXXX M XXXXXX K XXXXXX 'ITiiiiiJTiiiiilTinniTiijiiiTJiniiTiiiiii h iziiiiiiilllilllllliilllzlzlzlliiltzlzliii [0156] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each Fe-based metal plate were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the Sn content was 3.0 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 17. [0157] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/lk (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 17. [0158] [Table 17] - 82 - TABLE 17 I I .1 nviwn I ''ATIO OF I ACCUMULATION I ACCUMULATION I I I 1 CONDmON oj-rc a SINGLE DEGREE OF DEGREE OF B50 Bs „„,„ WlO/lk No. ,'^ PHASE (2001 PLANE {2221 PLANE (T) (T) "^'"^ (W/kg) ^^' W) (X) W ^___ COMPARATIVE g_.| Q Q ,3 ,3 , g, j.OB 0.78 91 EXAMPLE ___^_^^^ __—^^___ >——^^—.—^ — 6-2 6 02 30 10 1.75 2.06 0.85 64 EXAMPLE 6-3 43 KS 33 8 L7L ^"^ 0.85 56 OF 6-4 78 6;2 33 8 1.75 2.06 0.85 43 PRESENT 6-5 100 38 33 8 1.75 2.06 0.85 38 INVENTION 6-6 100 68 33 8 L75_ 2.06 0.85 43 6-7 100 87 33 8 1.75 2.06 0.85 58 '^°"^*['^™^ 6-8 0 0 13 13 1.61 2.06 0.78 92 EXAMPLE ^^_—^__^^^^_ ^^^^^—__^_^^ ■^.„—^ 6-9 7 OJ 43 4^2 1.79 2.06 0.87 61 cv«.iD, c 6-10 65 2.4 54 1.8 1.85 2.06 0.90 52 EXAMPLE ^.^-—— —» OF 6-11 85 5^9 54 VS 1^ 2.06 0.90 43 PRESENT 6-12 100 46 54 1L8 1^ 2.06 0.90 32 INVENTION 6-13 WO 72 54 1^8 1^ 2.06 0.90 35 6-14 100 90 54 1.8 1.85 2.06 0.90 52 '^^EXM^JE'^ 6-15 0 0 13 13 1.63 2.06 0.79 93 6-16 ' 6 " 0.2 64 27 1.90 2.06 0.92 61 cvAMDic 8-17 78 3.5 80 0.9 1.98 2.06 0.96 46 EXAMPLE ■— OF 6-18 92 8^2 80 09 1.98 2.06 096 40 PRESENT 6-19 100 38 80 09 1^ 2.06 096 28 INVENTION 6-20 100 69 80 09 1^ 2.06 0.96 32 6-21 100 85 60 0.9 1.98 2.06 0.96 48 °°"P^f^FE 6-22 0 0 13 13 1.61 2.06 0.78 98 EXAMPLE 6-23 5 Ol 30 10 1.75 2.06 085 64 EXAMPLE 6-24 68 2^2 31 9 1J3_ 2.06 0.84 59 OF 6-25 84 6.4 31 9 1J3_ 2.06 0.84 44 PRESENT 6-26 100 35 31 9 1.73 2.06 084 39 INVENTION ^^^~~~"~ 6-27 100 71 31 9 1.73 2.06 0.84 43 6-28 100 95 31 9 1.73 2.06 084 59 '^O";^;™^ 6-29 0 0 13 13 1.61 2,06 078 103 EXAMPLE __^^_^__ ^^_^^_^___^_ _^^^____^__ 6-30 5 2 42 4J 1.81 2.06 0.88 64 EXAMPLE 6-31 48 1^5 55 2^3 1^ 2.06 0.91 52 OF 6-32 77 6£ 55 2J 1^ 2.06 091 41 PRESENT 6-33 100 40 55 2.3 1.87 2.06 091 34 INVENTION 6-34 100 71 55 2^3 1^ 2.06 091 38 6-35 100 93 55 2.3 1.87 2.06 0.91 54 ""ETAM'^IL'^^ 6-36 0 __0 13 13 1,63 2.06 0.79 98 6-37 7 02 62 2J 1.92 2.06 0.93 ~ 63 ^XmPl£ 6-38 57 1^ 74 03 1^ 2.06 0.95 46 OF 6-39 79 7^6 74 03 1^ 2.06 0.95 42 PRESENT 6-40 100 43 74 03 1^ 2.06 095 29 INVENTION 6-41 100 74 74 03 V96_ 2.06 0.95 32 6-42 100 86 74 03 1.96 2.06 095 47 [0159] As listed in Table 16, in examples of the present invention (conditions No. 6-2 to No. 6-7, No. 6-9 to No. 6-14, No. 6-16 to No. 6-21, No. 6-23 to - 83 - No. 6-28, No. 6-30 to No. 6-35, No. 6-37 to No. 6-42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 17, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 17, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio BSO/Bs was 0.85 or more. [0160] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0161] (Seventh Experiment) In a seventh experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in - 84 - 42 kinds of manufacturing conditions (condition No. 7-1 to condition No. 7-42) were studied. [0162] Base metal plates (silicon steel plates) used in the seventh experiment contained components of the composition Q listed in Table 11 and inevitable impurities, with the balance being Fe . An actually-measured value of the A3 point at which the base metal plates used in the seventh experiment transformed to a y single phase was 1020°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 7-1 to the condition No. 7-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0163] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 ym from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 18. [0164] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes - 85 - in the a phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0165] Thereafter, Mo layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 7-1, No. 7-8, No. 7-15, No. 7-22, No. 7-29, and No. 7-36. Thickness of each of the Mo layers (total thickness on the both surfaces) is listed in Table 18. [0166] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 18. [0167] [Table 18] - 86 - pi 5ig£g= SSSSS8 2 ;asasa = isssss 2 sassss = ssssss = asssee !!!!_ || s ssssss 8 asssss s asssss S ssssss s ssssss s ssgsss MiHEEHnni:::!!::::!!!:::::::!:::::': ||5g = S222SS 2 sasaaa = 32222= 2 =.---- 2 sssss: = ssssss |IE::E;::E:E::-::::::;::::;;E:: I jg i i i I i i 1 i I I i I I § I i 1 i i I I ? i I I I ? ? ? I i i § I ? i i i § i § I §g2g , 222222 I ^^r-,.^^ 2 3SSS32 = 2 = = ~~2 2 -«o»-« I 55ri;;riS pi iin I |i_ g lie i i! I i I i 111 i i I i 11111 i i i i 1 i 11 i I i 1 i I i i! I i i 11 i 7 _IiZ::::::Z::::::Z::::::i::::::Z::::::I:;:::; E |1 S3S3SS ;3SSS3 33333; -«=... ...... ..--.. ^_£11 I I i I i || S SS8888 8888SS8 8881888 SS|SSSSSSSSSSS 8 SSSSSS i |-| =2 % % % % =2 % =2 =2 =2 =2 =2 =2 % =2 =S % % =2 =2 % =g =S % =2 =2 % =2 % =2 % =2 =2 =2 % 's % % % % % % 1^ I i|2 s s s s s s s £ S S S S g 5 s s s s s s s s s 8 s s s s 3 s S S s 2 K s s s 8 s s s 'TIiiiiiiT!liiilMHiiiTiiiiliiiJiiih""ii i I |l| HI I NI I HI If ^ [0168] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the Mo content was 3.8 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 19. [0169] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss W10/l]c (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 19. [0170] [Table 19] - 88 - TABLE 19 I I ii nviur I ''*"n° O"^ I ACCUMULATION I ACCUMULATION I I I I CONDITION ZrZn « SINGLE DEGREE OF DEGREE OF B50 Bs „„ ,„ WlO/lk No. ,J,^ PHASE (2001 PLANE (222) PLANE (T) CT) *^^"'"^ (W/kg) )2! 22 ^ £2 '^°^»r/^!!^T-'^^ 7-1 0 0 13 13 1.60 2.05 0.78 91 EXAMPLE ^___^^^_«^_ _—^.^.^-^._^_- ^_____^^_-_^_^^— ^^__ ^_„ ___»_ .^__-^— 7-2 8 02 30 10 1.74 2.05 0.85 62 EXAMPLE '-' !a__J:5 i] 12 LZLJ:2L_2i5 57_ OF 7-4 95 87 30 10 1.74 2.05 0.85 44 PRESENT 7-5 100 35 30 10 1.74 2.05 0.85 37 INVENTION 7-6 100 73 30 10 ^74_ 2.05 0.85 43 7-7 100 87 30 10 1.74 2.05 0.85 58 ^^"f.'^^'f;™^ 7-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE , 7-9 7 02 41 5^8 1.78 2.05 087 63 cvAwo, c 7-10 64 2.6 53 2.7 1.85 2.05 0.90 57 EXAMPLE —■ OF 7-11 94 TS 53 2J 1.87 2.05 091 42 PRESENT 7-12 100 42 53 ZJ 1.85 2.05 0.90 33 INVENTION 7-13 100 71 53 2J L£5_ 2.05 0.90 38 7-14 100 95 53 2.7 1.87 2.05 0.91 53 '=°"P*''*™E 7-15 0 0 13 13 1.62 2.05 0.79 93 IIAAMHLE ^^_^_^ 7-16 7 03 60 2S 1.91 2.05 0.93 61 cvAi.c. c 7-17 67 1.2 75 1.3 1.95 2.05 0.95 48 EXAMPLE ^ OF 7-18 89 5^9 75 M 1.93 2.05 0.94 41 PRESENT 7-19 100 37 75 1.3 1.95 2.05 0.95 28 INVENTION '—' 7-20 100 72 76 M 1.97 2.05 0.96 33 7-21 100 87 75 1.7 1.95 2.05 0.95 48 '^T/Tup^i''^ 7-22 0 0 13 13 1.60 2.05 078 98 EXAMPLE _„^.^^.^— __^_-_—«_-__ ^ 7-23 4 02 30 11 1.74 2.05 0.85 64 EXAMPLE 7-24 57 1^2 32 9 L74_ 2.05 085 56 OF 7-25 87 6J 32 9 U4_ 2.05 085 45 PRESENT 7-26 100 45 32 9 1.74 2.05 085 37 INVENTION 7-27 100 72 32 9 1.74 2.05 0.85 42 7-28 100 92 32 9 1.74 2.05 0.85 57 ''°ETAri,T' '-'' ° ° '2 13 1.60 2.05 0.78 100 7-30 8 02 43 4J 1.78 2.05 0.87 64 EXAMPLE 7-31 54 U 56 2J 1.87 2.05 0.91 52 OF 7-32 78 6J 56 2J 1.85 2.05 0.90 41 PRESENT 7-33 100 38 56 2.2 1.87 2.05 0.91 32 INVENTION 7-34 100 71 56 2J 1.85 2.05 O90 38 7-35 100 91 56 Z2 1.87 2.05 0.91 54 ^"STE""" 7-36 0 0 13 13 1.62 2.05 0.79 97 7-37 6 01 59 35 1.91 2.05 093 62 EXAMPLE 7-38 70 2^3 82 08 1.95 2.05 0.95 46 OF 7-39 91 7^1 82 08 1.95 2.05 0.95 40 PRESENT 7-40 100 41 82 08 1.97 2.05 0.96 26 INVENTION 7-41 100 76 S2. OB 1^ 2.05 0.95 32 7-42 100 100 82 0.8 1.97 2.05 0.96 48 [0171] As listed in Table 18, in examples of the present invention (conditions No. 7-2 to No. 7-7, No. 7-9 to No. 7-14, No. 7-16 to No. 7-21, No. 7-23 to No. 7-28, No. 7-30 to No. 7-35, No. 7-37 to No. 7- - 89 - 42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 19, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 19, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/BS was 0.85 or more. [0172] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0173] (Eighth Experiment) In an eighth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. - 90 - B-1 to condition No. 8-42) were studied. [0174] Base metal plates (silicon steel plates) used in the eighth experiment contained components of the composition R listed in Table 11 and inevitable impurities, with the balance being Fe. An actually-measured value of the A3 point at which the base metal plates used in the eighth experiment transformed to a y single phase was 1010°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 8-1 to the condition No. 8-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respect ively. [0175] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 ]im from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 20. [0176] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, - 91 - and it was found that, as rolled, the accumulation degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0177] Thereafter, V layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by an sputtering method, except in the conditions No. 8-1, No. 8-8, No. 8-15, No. 8-22, No. 8-29, and No. 8-36. Thickness of each of the V layers (total thickness on the both surfaces) is listed in Table 20. [0178] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 20. [0179] [Table 20] - 92 - \h% I I I I 3w2a 2 s.«-«- = 333SS5 = riS^ss; = =22222 2 5:-!;^:;:: 2 ssssss pi il!L || s sasasa s aaaasa 8 sasssa ~ ssssss a ssssss s ssssss |s| 2 22222S 2 222222 S 222222 S 252222 2 222222 2 222222 ii^s = =----- 2 SSS333 2 5:s = =-= 2 =22222 2 s:; ::•:::::: 2 5SSSSS PL IdB^g 2 SSSSfJH 2 ?SS5CE 2 SRPP2S 2 SSSS5S 2 USSSSSS 2 gSSESS ip. |ig i iiiiii i iiilil i iiiiii ! ii§!l! ! Illlll I iilill gg^ss 2222 = 2 2 .».«><.» 2 533353 2 = = = = = = 2 r-.-.-^^r- a sssSSS e ' |J8 1iiiiii I lllili I iliiii iiiiiiI Iiliili ililiii 7 h gl ,,,».» ,,,»•» ,,>.»«, 222222 2222S2 252222 1^1 i i i i i 2 S >>>>>> >>>>>> >>>>>> >>>>>> >>>>>> >>>>>> jl 2§8|8§|8ii88i§§li8S88SSSSSSSSSg8SgSSSgSS8S i|-| =2 =2 =2'2'2 =2 =2 '2 '2=2=2=2=2% =2 =2=2=5=2=5=2 =2 =5=5=5=2=2=2 =2 =2=2=2=5=2=2 =2 =2=2=5=5=2=5 Ogg X XXXXXX X XXXXXX X XXXXXX X XXXXXX X XXXXXX X XXXXXK I ||» S 8SSS8S S 5S5SSS s SSSSSS 8 SSSSSS 5 SSssSS 8 SSSSSS 'TIPOMinnin!!!!?!l!0!nlOiy!i!!!!!! o te Eoeccsea: oc tcicKKae e tr K tr. ec tr u tc a tc oc a x a tn K oc vc ac a tr a. a. cc tt cc. ec a. [0180] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the V content was 1.8 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 21. [0181] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/lk' (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 21. [0182] [Table 21] - 94 - TABLE 21 I I Ai nviMP I "AflO °^ I ACCUMULATION I ACCUMULATION I I I I CONDITION □,Tc " SINGLE DEGREE OF DEGREE OF B50 Bs WlO/lk No. ,1^ PHASE (2001 PLANE 1222) PLANE (D CD °°"' ' (W/kg) "^ (%) (%) (X) ^°^'V^!!^Tr'^ 8-1 0 0 13 13 1.60 2.05 0.78 91 EXAMPLE 8-2 8 07 30 12 1.74 2.05 0.85 62 cvAiiDic 8-3 82 1-5 31 10 1.74 2.05 0.85 57 EXAMPLE ■ • OF 8-4 95 87 30 10 1.74 2.05 0.85 44 PRESENT 8-5 100 35 30 10 ]Ji_ 2.05 0.85 37 INVENTION B-6 100 73 30 10 L74_ 2.05 0.85 43 8-7 100 87 30 10 1.74 2.05 0.85 58 '^".^J'.'^^T!^^ 8-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE ___^^^ 8-9 6 07 42 5J 1.76 2.05 0.86 61 rv..iDi,r 8-10 64 2.6 53 2.7 1.85 i05 0.90 57 EXAMPLE ' OF 8-11 94 7J 53 2J 1.87 2.05 0.91 42 PRESENT 8-12 100 42 53 TT L85_ 2.05 0.90 33 INVENTION 8-13 100 71__ 53 2.7 L85_ 2.05 0.90 38 8-14 100 95 53 2.7 1.87 2.05 0.91 53 •^""J"/^!^™^ 8-15 0 0 13 13 1.62 2.05 0.79 94 cXAIwPLc _^____«_^^^^^___ ^__—-^_^^.^^^_^_^ ,_ ^^^^ .^_^«^.^^ 8-16 7 03 59 3J 1.89 2.05 0.92 62 EXAMPLE 8-17 67 17 75 L3 1^ 2.05 0.95 48 OF 8-18 89 5;9 75 14 L93_ 2.05 0.94 41 PRESENT 8-19 100 37 75 L3 L95_ 2.05 0.95 28 INVENTION 8-20 100 72 76 14 L97_ 2.05 0.96 33 8-21 100 87 75 1.7 1.95 2.05 0.95 48 ''°r"v?u^l'^ 8-22 0 0 13 13 1.60 2.05 0.78 103 EXAMPLE 8-23 5 OJ 30 11 1.74 2.05 0.85 63 gj^j^pLg 8-24 57 17 32 9 U4_ 2.05 0.85 56 OF 8-25 87 17 32 9 174_ 2.05 0.85 45 PRESENT 8-26 100 45 32 9 1.74 2.05 0.85 37 INVENTION 8-27 100 74 32 9 1.74 2.05 0.8S 42 8-28 100 92 32 9 1.74 2.05 0.85 57 ""E'S'E''^ 8-29 0 0 13 13 1.60 2.05 0.78 102 8-30 8 OJ 43 5J 1.78 2.05 0.87 ~ 63 EXAMPLE 8-31 54 L3 56 2J 1.87 2.05 0.91 52 OF 8-32 78 6A 56 2J 1.85 2.05 0.90 41 PRESENT 8-33 100 38 56 27 1.87 205 0.91 32 INVENTION 8-34 100 71 58 2J L85_ 2.05 0.90 38 8-35 100 91 56 2.2 1.87 2.05 0.91 54 ""^"^I^" 8-36 0 0 13 13 1.62 2.05 0.79 99 8-37 5 OJ 62 2.1 1.89 2.05 O.9I 62 ~ g)(^j^pL£ 8-38 70 23 82 OB L95_ 2.05 0.95 46 OF 8-39 91 TA 82 08 L95_ 2.05 095 40 PRESENT 8-40 100 41 82 08 L97_ 2.05 0.96 26 INVENTION 8-41 100 76 82 08 L95_ 2.05 0.95 32 8-42 100 100 82 0.8 1.97 2.05 096 48 [0183] As listed in Table 20, in examples of the present invention (conditions No. 8-2 to No. 8-7, No. 8-9 to No. 8-14, No. 8-16 to No. 8-21, No. 8-23 to - 95 - No. 8-28, No. 8-30 to No. 8-35, No. 8-37 to No. 8-42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 21, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 21, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio BSO/Bs was 0.85 or more. [0184] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss W10/l}c maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0185] (Ninth Experiment) In a ninth experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in - 96 - W2. kinds of manufacturing conditions (condition No. 9-1 to condition No. 9-42) were studied. [0186] Base metal plates (silicon steel plates) used in the ninth experiment contained components of the composition S listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the ninth experiment transformed to a Y single phase was 1080°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 9-1 to the condition No. 9-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0187] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 ijm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 22. [0188] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, - 97 - and it was found that, as rolled, the accumulation degree of the {200} planes in the a. phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0189] Thereafter, Cr layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by an electroplating method, except in the conditions No. 9-1, No. 9-8, No. 9-15, No. 9-22, No. 9-29, and No. 9-36. Thickness of each of the Cr layers (total thickness on the both surfaces) is listed in Table 22. [0190] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 22. [0191] [Table 22] - 98 - §1 il!i || s S5SXSX s SSS5SS s sassss a ssssss a ssssss s ssssss |2g5 = = = = = = 2 55555S = 3SS5S3 e 2----- 2 253333 = ~SS5S3 u ||g I I 11 I § 5 5 I I 11 I I § I g S I I g i 111 i I I I I 111 I I I I i 11 I I 3gJg2 222 = 22 2 .«»»».«« 2 riririririS = 2~222= 2 „« = .»« 2 333333 pi ^ : fie i I i i i i i i i i i i i i i i i i i i I i i i i i i i i i i i i i i I i i i i i I "^ : ii -:::::r:::::r:::::r:::::r::::::-:::::: S-V i ' ' ' ^ ^ ^1 &665&6 66S6&6 i i a 6 6 & 6 6 6 6 6 6 6 6 6 6 6 6 diiiiSi 11 8888888 8888888 8888888 gSgSSggSSgSSSg gSSgSSg ig-7 % % % % % % % % % % > =o =o % % % \ =, \ % == % % % % % =2 =o == % % \ % '= '= '= % % \ \ \ =S 5i I ||8 S 8S8SSS S 222222 s SSSSSS S SSSSSS 2 iSssSi 8 SSS2SS 'Tliiiiliilmn=i"i»Tiiniiili!iliiii»" fi iiiiiiiiiUiUiliUUtllUUliUUiliUiii ^1 pHillHtHHiJN [0192] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the Cr content was 13.0 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 23. [0193] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/llc (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 23. [0194] [Table 23] - 100 - TABLE 23 I I 411 nviNO I ^^° °^ I ACCUMULATION I ACCUMULATION I I [ I CONDITION '^'-p"J['"^ or SINGLE DEGREE OF DEGREE OF B50 Bs „„,„ WlO/lk No. f'^ PHASE {2001 PLANE {2221 PLANE (T) (T) "*"^"« (W/kg) ^ ' (X) (%^ 2S^ T)Cnjr ^-^ ° ° '^ 13 L60 2.05 0.7B 95 9-2 6 0^2 30 10 1.74 2.05 0.85 62 EXAMPLE 9-3 82 L5 31 10 U4_ 2.05 0.85 57 OF 9-4 95 8^2 30 10 U4_ 2.05 0.85 44 PRESENT 9-5 100 35 30 10 1.74 2.05 0.85 37 INVENTION 9-6 100 73 30 10 1.74 2.05 0.85 43 9-7 100 87 30 10 1.74 2.05 0.85 58 '^T)UMPL™^ 9-8 0 0 13 13 1.60 2.05 0.78 93 9-9 10 04 46 4^8 1.78 2.05 0.87 61 EXAMPLE 9-10 64 2^6 53 2^7 L85_ 2.05 0.90 57 OF 9-11 94 7J 53 27 L87_ 2.05 0.91 42 PRESENT 9-12 100 42 53 2.7 1.85 2.05 0.90 33 INVENTION 9-13 100 71 53 27 1.85 2.05 0.90 38 9-14 100 95 53 27 1.87 2.05 0.91 53 ''°p"Jl'!:l^^^ 9-15 0 0 13 13 1.62 2.05 079 94 EXAMPLE ^^_^___ _^_^___ _^^^^^_ ..^^^^___^__ _^^_^^____ ^___ 9-16 9 03 61 2^3 1.89 2.05 0.92 62 EXAMPLE 9-17 67 L2 75 L3 TM_ 2.05 0.95 48 OF 9-18 89 59 75 M L93_ 2.0S 094 41 PRESENT 9-19 100 37 75 1.3 1.95 2.05 095 28 INVENTION " 9-20 100 72 76 L4 1.97 2.05 096 33 9-21 100 87 75 17 1.95 Z05 095 48 °°,^J'»'^^^^ 9-22 0 0 13 13 1.60 2.05 0.78 98 EXAMPLE __^^^_^ 9-23 6 02 30 12 1.74 ^05 085 65 EXAMPLE 9-2< 57 L2 32 9 174_ 2.05 0.85 56 OF 9-25 87 67 32 9 174_ 2.05 0.85 45 PRESENT 9-26 100 « 32 9 174_ 2.05 0.85 37 INVENTION 9-27 100 72 32 9 174_ 2.05 0.85 42 9-28 100 92 32 9 1.74 2.05 0.85 57 ^°^fl'!jt™^ 9-29 0 0 13 13 1.60 2.05 0.78 96 EXAMPLE 9-30 5 01 42 5;2 1.78 2.05 087 64 cvA.inic 9-31 54 1.3 56 2.1 1.87 2.05 0.91 52 EXAMPLE OF 9-32 78 6J 56 2J L85_ 2.05 0.90 41 PRESENT 9-33 100 38 56 2^2 1£7_ 2.05 091 32 INVENTION 9-34 100 71 56 2J 1^ 2.05 O90 38 9-35 100 91 56 2.2 1.87 2.05 091 54 *^°"J'*!!^^ 9-36 0 0 13 13 1.62 2.05 079 100 EXAMPLE 9-37 5 01 62 2 1.89 2.05 0.92 64 ^XAf^pf_^ 9-38 70 2^3 82 08 r95_ 2.05 09S 46 OF 9-39 91 7J 82 08 L95_ 2.05 0.95 40 PRESENT 9-40 100 41 82 08 1.97 2.05 096 26 INVENTION 9-41 100 76 82 08 1.95 2-05 0.95 32 9-42 100 100 82 08 1.97 2.05 096 48 [0195] As listed in Table 22, in examples of the present invention (conditions No. 9-2 to No. 9-7, No. - 101 - 9-9 to No. 9-14, No. 9-16 to No. 9-21, No. 9-23 to No. 9-28, No. 9-30 to No. 9-35, No. 9-37 to No. 9-42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 23, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 23, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio BSO/Bs was 0.85 or more. [0196] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0197] (Tenth Experiment) In a tenth experiment, correlations between an accumulation degree of {200} planes and an - 102 - accumulation degree of {222} planes and core loss in 42 kinds o.f manufacturing conditions (condition No. 10-1 to condition No. 10-42) were studied. [0198] Base metal plates (silicon steel plates) used in the tenth experiment contained components of the composition T listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the tenth experiment transformed to a Y single phase was 1020°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 10-1 to the condition No. 10-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0199] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 ]jm from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 24. [0200] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes - 103 - in the a phase were measured by the aforesaid method, and it was found that, as rolled, the accumulation degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0201] Thereafter, Ti layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 10-1, No. 10-8, No. 10-15, No. 10-22, No. 10-29, and No. 10-36. Thickness of each of the Ti layers (total thickness on the both surfaces) is listed in Table 24. [0202] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes of the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 24. [0203] [Table 24] - 104 - hi il!L |i s 5SSSSS s 5SSSSS s ssassa g ssssss s sssgss s ssssss JI^T::::::7::::::T::::::7::::::7::::::7:::::: i|i |ig 111111111111111111111111IIIIII III 11II g IIII ii i ilig = s s B s s s ... s s . s = = = = = = = = s s s s s s .. s s . s s s s s s s s s |L_ g lie i i i I i i i i i i i i i I i i i i I i I I i I i i 11 i I i i 11 i I I i i i i i ° _]|7;;;;;;7;;;;;;7;;;;;;7;;;^ « i| „„,«««« ,«««>««» ,»„m-.».^ SSSSSS SSSSSS ssssss l_tl I 1 1 1 _—__ i 1 ll iSiii|88888|S888888888SSaSgS8gS|SgSSSSSSSg h'l % =S=2=S=2=S=2 =2 =2=2=S'2=2=2 % \%\%\% % %\%%^% % =S =S =2 =S =S % % =2 %'2'g =='o 111 i ;;;;;: i ;;;;;; !S Jiss;^ ; ;;;;;; ; :;ii;; 5 siSiSi I i|2 3 S S S S 8 8 S S = 2 S 2 5 s S S S 8 S S S S S S S S S = S S 5 5 s S S S S IS S S S p t- HKi-l-l-H (- l-l-Kl-t-H K Kh-t-HKt- K t-t-KKl-t- I- KKKHf-K (- |-h-HI-l-|~ h luiuiuimnumttnnntinmnnni [0204] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the Ti content was 1.2 mass% or more was regarded as the a single phase region, and a ratio of the a. single phase region was found from the aforesaid expression (4). Results of these are listed in Table 25. [0205] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/lk (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 25. [0206] [Table 25] - 106 - TABLE 25 I I Ai nviNr I '^^'^ °'' I ACCUMULATION I ACCUMULATION I I I I CONDITION o"ZI: Of SINGLE DEGREE OF DEGREE OF B50 Bs W10/1k No. ,1 PHASE {2001 PLANE 1222} PLANE (T) (T) """^"^ (yy/kg) ''^ (« (tt 2S2 . '^°"j'*'^^ 10-1 0 0 13 13 1.60 2.05 0.78 91 10-2 6 02 30 LI 1.74 2.05 0.B5 62 EXAMPLE tO-3 82 L5 31 10 1.74 2.05 0.85 57 OF 10-4 95 8^2 30 10 1.74 2.05 0.85 44 PRESENT 10-5 100 M 30 ^0 1.74 2.05 0.85 37 INVENTION 10-6 100 73 30 10 L74_ 2.05 0.85 43 10-7 100 87 30 10 1.74 2.05 0.85 58 °?v1u'^r^ 10-8 0 0 13 13 1.60 2.05 0.78 93 EXAMPLE ^^________^^ 10-9 8 02 41 5J 1.76 2.05 0.86 62 EXAMPLE '0-tO 64 2^6 53 2^7 L85_ 2.05 0.90 57 OF 10-11 94 7^8 53 2J 1.87 2.05 091 42 PRESENT 10-12 100 42 53 2.7 1.85 2.05 O90 33 INVENTION ~ " 10-13 100 71 53 zn 1.85 2.05 0.90 38 10-14 100 95 53 2.7 1.87 2.05 091 53 <=°"'l*f^™E 10-15 0 0 13 13 1.62 2.05 079 92 EXAMPLE 10-16 7 03 64 L8 1.91 2.05 0.93 61 g^j^pi_g 10-17 67 1L2 75 L3 1.95 2.05 0.95 48 OF 10-18 89 5^9 75 M 1.93 2.05 094 41 PRESENT 10-19 100 37 75 L3 1.95 2.05 095 28 INVENTION 10-20 100 72 76 L4 L97_ 2.05 096 33 10-21 100 87 75 1.7 1.95 Z.05 0.95 48 °°"P'\f^^ 10-22 0 0 13 13 1.60 2.05 0,78 102 EXAMPLE __^^__^^_ ^_™_^ 10-23 8 03 30 n 1.74 2.05 0.85 65 EXAMPLE 10-24 57 L2 32 9 1.74 2.05 0.85 56 OF 10-25 87 67 32 9 1.74 2.05 0.85 45 PRESENT 10-26 100 45 32 9 1.74 2.05 085 37 INVENTION 10-27 100 72 32 9 L74_ 2.05 085 42 10-28 100 92 32 9 1.74 2.05 085 57 ^"""V^I^Tf^ 10-29 0 0 13 13 1.60 2.05 0,78 99 EXAMPLE 10-30 5 01 42 4^2 1.78 2.05 087 65 rvAiiD. c 10-31 54 1.3 56 2.1 1.87 2.05 0.91 52 EXAMPLE —— OF 10-32 78 6J 56 2J r£5_ 2.05 0,90 41 PRESENT 10-33 100 38 56 2.2 1.87 2.05 0.91 32 INVENTION ~"^—' ■"" 10-34 100 71 56 2J 1.85 2.05 O90 38 10-35 100 91 56 2.2 1.87 2.05 0.91 54 '^°"'VJ!'*™^ 10-36 0 0 13 13 1.62 2.05 079 97 EXAMPLE 10-37 4 01 63 VS 1,91 2,05 0.93 62 EXAMPLE 10-38 70 2^3 82 08 1.95 2.05 0.95 46 OF 10-39 91 7J 82 08 1,95 2.05 0,95 40 PRESENT 10-40 100 41 82 0.8 1.97 2.05 0.96 26 INVENTION ~~~^^~~~ ^—_-_^— 10-41 100 76 82 08 1,95 2.05 095 32 10-42 100 100 82 0.8 1,97 2,05 0.96 48 [0207] As listed in Table 24, in examples of the present invention (conditions No. 10-2 to No. 10-7, No. 10-9 to No. 10-14, No. 10-16 to No. 10-21, No. 10-23 to No. 10-28, No. 10-30 to No. 10-35, No. 10-37 - 107 - to No. 10-42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 25, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 25, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/Bs was 0.85 or more. [0208] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0209] (Eleventh Experiment) In an eleventh experiment, correlations between an accumulation degree of {200} planes and an accumulation degree of {222} planes and core loss in 42 k:inds of manufacturing conditions (condition No. - 108 - 11-1 to condition No. 11-42) were studied. [0210] Base metal plates (silicon steel plates) used in the eleventh experiment contained components of the composition U listed in Table 11 and inevitable impurities, with the balance being Fe. An actually-measured value of the A3 point at which the base metal plates used in the eleventh experiment transformed to a y single phase was 1000°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 11-1 to the condition No. 11-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0211] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 \im from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 26. [0212] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, - 109 - and it was found that, as rolled, the accumulation degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0213] Thereafter, Ga layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a vapor deposition method, except in the conditions No. 11-1, No. 11-8, No. 11-15, No. 11-22, No. 11-29, and No. 11-36. Thickness of each of the Ga layers (total thickness on the both surfaces) is listed in Table 26. [0214] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 26. [0215] [Table 26] - 110 - g5;g s 22SH22 = 5S5SSS = 35:^52:= = = = 2S5= 5 33S3SS = "SSSSS il t~E:::::EE:::E;:::::::::::: II sssssssssssssssssssssasssssissssssssssssgs S als s 2SSSS2 = ;sssss = 325s::?s = = = = 55= = ssssss = -sssss - ligSg n gsasss = sssaais = ssssss = 3^5 = 55 s SSSSSK = ssssss ||i I jg i 111111 I I i 1111 I 11 i I i I I 11 f I! I I 111!!! i i 111 i I ii:;;;:;;:;;;;;;:;;;;;;:;;;;:;::::;;:;;;:; , g_ ^ ije i iiiiii i iiiiii i iiiili iliiili § iiilil i iiilii ^ III 2 S22222 2 2222S2 2 222222 2 2SS222 2 222222 S 2222S2 b ^I = = «.•«• «««»«o «,„«eu>. ;rs:;« i:;;is ;;rr?i IJ_t I I I I i II s i i § s i i i iiiiii § iiiiii g s s s s s g s g s s s s § s s g s § s g ii"-i % \%\\%% % %'k\%\S \ %%%%%% % =2=2 "2 =2 =2 =2 =2 =2'S^2=2V> % %%%%%% I pg s a s a 8 s s S S S 5 £ S 5 a s s a s s s s s s s s s s 5 S 5 S S g S s 8 s s s s a TIOHOlOOOl!!!!!!lOinyOE!!!!!! 1^ liiiiiiiiizininiiliziniiitififiiiiiiiii [0216] Further, an alloying ratio of the metal layer and a ratio of the a single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the Ga content was 4.1 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 27. [0217] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/lk (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 27. [0218] [Table 27] - 112 - TABLE 27 I I 41 nviwr I "^^O °^ I ACCUMULATION I ACCUMULATION I i I I CONDmON O°TI: or SINGLE DEGREE OF DEGREE OF B50 Bs „.„ W10/1k No. "^T^ PHASE {2001 PLANE |2Z2l PLANE (T) (T) """^"^ (W/kg) ^J^ (%^ 00 «) COMPARATIVE ,,_, Q Q ^3 ,3 ,50 305 0 73 33 EXAMPLE 11-2 5 OJ 30 10 1.74 2.05 0.85 63 cv...o,t: ~3 82 il 31 10 1.74 2.05 0.85 57 EXAMPLE OF 11-4 95 8^2 30 10 r74^ 2.05 0.85 44 PRESENT 11-5 100 35 30 10 U4_ 2.05 0.85 37 INVENTION 11-6 100 73 30 10 VM_ 2.05 0.85 43 11-7 100 87 30 10 1.74 2.05 0.85 58 "^^.IT/^^I^Tl^^ 11-8 0 0 13 13 1.60 2.05 0.78 92 EXAMPLE _______^__ ______^^_^_ ____ 11-9 8 02 42 4^8 1.78 2.05 0.87 62 EXAMPLE 11-10 64 2.6 53 2^7 1^ 2.05 0.90 57 OF 11-11 94 7;8 53 2J 1^ 2.05 0.91 42 PRESENT 11-12 100 42 53 27 ^85_ 2.05 0.90 33 INVENTION 11-13 100 71 53 2J 1^ 2.05 0.90 38 11-14 100 95 53 27 1.87 2.05 0.91 53 '^°"J'.'^^^T!^ 11-15 0 0 13 13 1.62 2.05 0.79 92 EXAMPLE 11-16 5 02 59 2;9 1.87 2.05 0.91 63 cvAiin, c 11-17 67 1.2 75 1.3 1.95 2.05 0.95 48 EXAMPLE ■^^—^-—^— OF 11-18 89 5^9 75 L4 L93_ 2.05 0.94 41 PRESENT 11-19 100 37 75 1.3 1.95 2.05 0.95 28 INVENTION invcnuuiM 11-20 100 72 76 1J; 1.97 2.05 0.96 33 11-21 100 87 75 1.7 1.95 2.05 0.95 48 °°,5t''»'^!)^^^ 11-22 0 0 13 13 1.60 2.05 0.78 101 EXAMPLE 11-23 4 02 30 1J 1.74 2.05 0.85 64 EXAMPLE 11-24 57 17 32 9 1J4_ 2.05 0.85 56 OF 11-25 87 67 32 9 174_ 2.05 0.85 45 PRESENT 11-26 100 45 32 9 1.74 2.05 0.85 37 INVENTION 11-27 100 72 32 9 1.74 2.05 0.85 42 11-28 100 92 32 9 1.74 2.05 0.85 57 ""E'SLT^ n-29 0 0 13 13 1.60 2.05 0.78 97 11-30 9 04 45 42 1.80 2.05 0.88 63 gjy^j^pLg 11-31 54 L3 56 2J L87_ 2.05 091 52 OF 11-32 78 6J 56 2J L85_ 2.05 0.90 41 PRESENT 11-33 100 38 56 22 L87_ 2.05 0.91 32 INVENTION 11-34 100 71 56 2J L85_ 2.05 O90 38 11-35 100 91 56 2.2 1.87 2.05 091 54 T)SL'^L?^ 11-36 0 0 13 13 1,62 2.05 0.79 100 11-37 9 02 58 ~ 3 ~ 1.91 ToT 0.93 64 gj(^^,pL£ 11-38 70 2^3 82 08 155_ 2.05 095 46 OF 11-39 91 7J 82 08 1^ 2.05 0.95 40 PRESENT 11-40 100 41 82 0.8 1.97 2.05 096 26 INVENTION 11-41 100 76 82 08 1.95 2.05 095 32 11-42 100 100 82 0.8 1.97 2.05 096 48 [0219] As listed in Table 26, in examples of the present invention (conditions No. 11-2 to No. 11-7, - 113 - No. 11-9 to No. 11-14, No. 11-16 to No. 11-21, No. 11-23 to No. 11-28, No. 11-30 to No. 11-35, No. 11-37 to No. 11-42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 27, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 27, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio BSO/Bs was 0.85 or more. [0220] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0221] (Twelfth Experiment) In a twelfth experiment, correlations between an accumulation degree of {200} planes and an - 114 - accumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 12-1 to condition No. 12-42) were studied. [0222] Base metal plates (silicon steel plates) used in the twelfth experiment contained components of the composition V listed in Table 11 and inevitable impurities, with the balance being Fe. An actually-measured value of the A3 point at which the base metal plates used in the twelfth experiment transformed to a y single phase was 1000°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 12-1 to the condition No. 12-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0223] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 jam from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 28. [0224] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a - 115 - phase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, it was found that, as rolled, the accumulation degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0225] Thereafter, Ge layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 12-1, No. 12-8, No. 12-15, No. 12-22, No. 12-29, and No. 12-36. Thickness of each of the Ga layers (total thickness on the both surfaces) is listed in Table 28. [0226] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 28. [0227] [Table 28] - 116 - l^g ? =st!2 = s = ;2SS3S = 322332 = 2::::: = ;:!252: s 5SSSSS ii ilfi -_- || gs5sss5gs5sasssssss5sa5SS = S=s5sssgsasss§ss isdge = = ~a22 2 5S3SS2 = S22222 = 23i;is 2 55352" s SSSS3S pi iaffiS?. 2 888888 2 3SSSSS 2 ^SPPKP 2 S33SSS 2 5SSSSS 2 SPSSSS i!!i - i|g I I I § I I g I I I I I I I i I i i i I i I I ? I I S I I I I I S g S S I I I I ? g ||Sg 2 2SSS22 2 222555 3 S35SSS 2 E = C = = = S ,,,,,, 2 SS33ri3 fa_ i Si^S = SlSi^SSS 2 S!!SS88 = SSSSSS = SSiSSE:^ 2 39393S :: SSSSSS |l! I—-; r- gi ^ pH i iiiiii i iiiiii i iiilii i iiiiii i iiiiii i iiiili ^ i| I 5 S^ ^^,^r.^r. ^^r.r-r.|~ „^n.r.-.„ PtCTTC^Ct EC:E~=~ =~::~ = :: ^^1 I I I I I ^ I 55535.S 5 5 S S S S S S S S 3 S S S S 3 S S 333333 33S333 il 8iii8i8888i88888S8888aS8SSSSgg88g8gg§gSS|g I i "S =2 % =2 =5 =2 % % =2 =g =5 =2 =2 % =2 =2 '2 % % % % % % % % % % % % % % =2 % % % % % % % % % % '2 55 6 » XXXXXK K XXXXXai X XXXXKX X XXXXXX X XXXXXX X MXXXXX I pg s a s s s s s s 5 s = S i s s s s s s s s a s s s s s s s s = § s s s s s s a s a s 'TTiiiliHiimhiin'Mmniyijjfjhiiii" I[:::;::::Z:;;:;;:Z:;:;;;;:;;;::::;;;:;; I n|Hi I H!| Hi I M [0228] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the Ge content was 6.4 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 29. [0229] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/lk (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 29. [0230] [Table 29] - 118 - TABLE 29 I I Ai I nviNP I ''*""° °^ I ACCUMULATION I ACCUMULATION I I I I CONDITION P4T!T: a SINGLE DEGREE OF DEGREE OF B50 Bs WlO/lk No. ,'. PHASE (2001 PLANE (222) PLANE (T) (T) *^^°''^^ (W/kg) ^^' (%) {%) (X) ""^E^^mi^^ '2-1 0 0 la 13 1.60 2.05 0.78 94 12-2 5 ai 30 U 1.74 2.05 0.85 64 EXAMPLE 12-3 82 1^5 31 10 U4_ 2.05 0.85 57 OF 12-4 95 8;2 30 10 1^ 2.05 0.85 44 PRESENT 12-5 100 35 30 10 U£ 2.05 0.85 37 INVENTION 12-6 100 73 30 10 L74_ 2.05 0.85 43 12-7 100 87 30 10 1.74 2.05 0.85 58 "^TXMJPLE^ 12-8 0 0 13 13 1.60 2.05 0.78 93 12-9 7 02 42 4ji 1.82 2.05 0.89 62 EXAMPLE 12-10 75 . 2.6 53 2^ 1^ 2.05 0.90 57 OF 12-11 94 re 53 2.7 1.87 2.05 0.91 42 PRESENT 12-12 100 42 53 2.7 1.85 2.05 0.90 33 INVENTION ' 12-13 100 71 53 2J 1.85 2.05 0.90 38 12-14 100 95 53 2.7 1.87 2.05 0.91 53 TST^ 12-15 0 0 13 13 1.62 2.05 0.79 95 12-16 7 02 61 2A 1.91 2.05 093 61 EXAMPLE 12-17 67 L2 75 1^3 1£5_ 2.05 0.95 48 OF 12-18 89 5S 75 1_4 1^ 2.05 0.94 41 PRESENT 12-19 100 37 75 1_3 L95_ 2.05 095 28 INVENTION 12-20 100 72 76 L4 L97_ 2.05 096 33 12-21 100 87 75 1.7 1.95 2.05 0.95 48 '^°E)WMPL£^^ '^"22 ° ° ^ '^ '■*° 2°^ °'^* '* 12-23 10 03 30 10 1.74 2.05 085 64 cvAiinm 12-24 57 1.2 32 9 1.74 2.05 0.85 56 EXAMPLE OF 12-25 87 6J 32 9 L74_ 2.05 085 45 PRESENT 12-26 100 45 32 9 1.74 2.05 085 37 INVENTION ^"~~~~~~ iiNVCMUun 12-27 100 72 32 9 1.74 2.05 0.85 42 12-28 100 92 32 9 1.74 2.05 085 57 ^°DCAMPLE^^ 12-29 0 0 13 13 1.60 2.05 078 104 12-30 5 01 43 4^9 1.78 2.05 087 63 rvAKoic 12-31 54 1.3 56 2.1 1.87 2.05 0.91 52 EXAMPLE —^-^^^ __-^^_^^__ . ^—^^— OF 12-32 78 6J 56 2J L85_ 2.05 0.90 41 PRESENT 12-33 100 38 56 12 L87_ 2.05 091 32 INVENTION 12-34 100 71 56 2J L85_ 2.05 0.90 38 12-35 100 91 56 2,2 1.87 2.05 091 54 °°E)UMPLE^^ 12-36 0 0 \1 13 1.62 2.05 0.79 98 12-37 6 03 58 2^8 1.89 2.05 " 092 63 gjj^j^pi^g 12-38 70 2^3 82 08 L95^ 2.05 0.95 46 OF 12-39 91 7J 82 08 L95_ 2.05 0.95 40 PRESENT 12-40 100 41 82 08 1.97 2.05 0.96 26 INVENTION ~^^~~~~~~ ~~^~~~~' ""^^^^~~~^~ ' 12-41 100 76 82 08 1.95 2.05 095 32 12-42 100 100 82 08 1.97 2.05 096 48 [0231] As listed in Table 28, in examples of the present invention (conditions No. 12-2 to No. 12-7, - 119 - W). 12-9 to No. 12-14, No. 12-16 to No. 12-21, No. 12-23 to No. 12-28, No. 12-30 to No. 12-35, No. 12-37 to No. 12-42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 29, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 29, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio B50/BS was 0.85 or more. [0232] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. [0233] (Thirteenth Experiment) In a thirteenth experiment, correlations between an accumulation degree of {200} planes and an - 120 - aT:cumulation degree of {222} planes and core loss in 42 kinds of manufacturing conditions (condition No. 13-1 to condition No. 13-42) were studied. [0234] Base metal plates (silicon steel plates) used in the thirteenth experiment contained components of the composition W listed in Table 11 and inevitable impurities, with the balance being Fe. An actually measured value of the A3 point at which the base metal plates used in the thirteenth experiment transformed to a y single phase was 1010°C. The base metal plates were fabricated in the same manner as that in the fourth experiment. In the condition No. 13-1 to the condition No. 13-42, cold rolling was performed in the same manners as those in the condition No. 4-1 to the condition No. 4-42 respectively. [0235] Next, dislocation density of each of the base metal plates was measured with a transmission electron microscope as in the first experiment. Here, in each of the base metal plates having undergone the blasting, since a texture with high dislocation density was observed in a region 30 jam from the surface, dislocation density in this region was measured. Average values of the obtained dislocation densities are listed in Table 30. [0236] Textures of the base metal plates at room temperature were observed, and it was found that their main phase was an a phase. Further, the accumulation degree of the {200} planes in the a - 121 - IBase and the accumulation degree of the {222} planes in the a phase were measured by the aforesaid method, it was found that, as rolled, the accumulation degree of the {200} planes in the a phase was within a 17% to 24% range and the accumulation degree of the {222} planes in the a phase was within a 17% to 24% range in each of the base metal plates. [0237] Thereafter, W layers as the metal layers were formed on a front surface and a rear surface of each of the base metal plates by a sputtering method, except in the conditions No. 13-1, No. 13-8, No. 13-15, No. 13-22, No. 13-29, and No. 13-36. Thickness of each of the W layers (total thickness on the both surfaces) is listed in Table 30. [0238] Subsequently, heat treatment was applied on the base metal plates on which the metal layers were formed, under various conditions as in the first experiment. Further, three samples were prepared per condition and the accumulation degree of the {200} planes in the a phase and the accumulation degree of the {222} planes in the a phase were measured at three stages of the heat treatment, as in the first experiment. Results of these are listed in Table 30. [0239] [Table 30] - 122 - hi pi 2^»2g 2 gSSSSS 2 5KSEKK 5 S3SSSS = SS5SSS ? ^SSSSS S SSSSSS2 i!!i - || s ssssss s SS35SS s sssass s ssssss s ssssgi s ssssss igsg = =,--»- 5 S55S5~ = ~SSSS5 2 -2SS22 e 2--"S" 2 2SSSSS pi i"^ ||g i I ? ? i ? ? ? I ? § S I § g i I I I g 2 I I I i I I i I § § I i i i i 11 i i i i ^|SB 2 223222 2 -o--.« S S2SSSS 2 222222 ; 222222 : 3Sri3SS pi 23SJg . 55S5KS 2 ;;;55; 2 sissss 2 ssssss 2 ssssss 2 ssssss 5^-- : IJE liiiiil iliiiilliiilll i iiiill I iiilll I illlil Si _|I7::::::7::::::7::::::7::::::T^ s 11 2?222t? ~::!5:^~-2 ::;5r!222 „o^„„o „„„„oo „„„..„„ ^J^ I I I i i I ^ g ££?£££ SSSSSf 33SS3S SSSS3S £3¥»?X SSSSSS |l S8Sg8SgSgS8ggg|8S8888SSaS8SSgSa8ggSggg|8Sg 1^-1 =2 =2 =2 °2 =2 =2 '2 % % \ % =2 =2 V =2 V % % 's '= =2 \ \ % \ \ \ % % % S % % \ \ \ \ \ % \ \ i4 TIiyyiOOEl!!!!!!iyOH!iMii!!!!!! ^ s ssssss s ssssss s ssssss s ssssss s ssssss s ssssss i| I HI III HI p Hip [0240] Further, an alloying ratio of the metal layer and a ratio of an a single phase region in each of the Fe-based metal plates were measured as in the first experiment. Here, in finding the alloying ratio, a region where the Fe content was 0.5 mass% or less and the content of ferrite former was 99.5 mass% or more was regarded as an alloy layer. Further, a region where the W content was 6.6 mass% or more was regarded as the a single phase region, and a ratio of the a single phase region was found from the aforesaid expression (4). Results of these are listed in Table 31. [0241] Further, as in the first experiment, magnetic flux density B50 and saturation magnetic flux density Bs were measured and a ratio B50/Bs of the magnetic flux density B50 to the saturation magnetic flux density Bs was calculated. Further, core loss WlO/lk (WlO/1000) at a 1000 Hz frequency when the magnetic flux density was 1.0 T was measured. Results of these are listed in Table 31. [0242] [Table 31] - 124 - TABLE 31 I I Al I OYlwr I ^""° °^ I ACCUMULATION I ACCUMULATION I I I I CONDITION '^'-^™^ Of SINGLE DEGREE OF DEGREE OF B50 Bs WlO/lk No. f'. PHASE {200J PLANE (222} PLANE (T) (T) "='"'^"s (W/kg) ^*' ()i) (W (W ^^_ ''°"J'/JJ^™^ 13-1 0 0 13 13 1.60 2.05 0.78 91 EXAMPLE 13-2 7 07 30 11 1.74 2.05 0.85 63 cvAnDic 13-3 82 1.5 31 10 1.74 2.05 0.85 57 EXAMPLE —— OF 13-4 95 82 30 10 U4_ 2.05 0.85 44 PRESENT 13-5 100 35 30 10 1.74 2.05 0.85 37 INVENTION "'"' 13-6 100 73 30 10 1.74 2.05 0.85 43 13-7 100 87 30 10 1.74 2.05 0.85 58 °°^'^'^!!^L'^^ 13-8 0 0 13 13 1.60 2.05 0.78 92 EXAMPLE __^^^___ _^^^__ 13-9 10 03 43 5^9 1.78 2.05 0.87 61 cvAMnic 13-10 64 2.6 53 2.7 1.85 2.05 0.90 57 EXAMPLE — —^^—.^ _———. OF 13-11 94 78 53 27 1£7_ 2.05 0.91 42 PRESENT 13-12 100 42 53_ 27 L85^ 2.05 0.90 33 INVENTION 13-13 100 71 53 27 L85_ 2.05 0.90 38 13-14 100 95 53 2.7 1.87 2.05 0.91 53 '^°"'',^?^™^ 13-15 0 0 13 13 1.62 2.05 0.79 92 EXAMPLE 13-16 5 OJ 63 2 1.91 2.05 0.93 63 cvAwn. c 13-17 67 1.2 75 1.3 1.95 2.05 0.95 48 EXAMPLE ^^^—— ——^^^ —— ~^—— OF 13-18 89 5^9 75 L4 L93_ 2.05 0.94 41 PRESENT 13-19 100 37 75 1^3 L95_ 2.05 0.95 28 INVENTION 13-20 100 72 76 L4 L97_ 2.05 0.96 33 13-21 100 87 75 17 1.95 2.05 0.95 48 °°^''.'^!!^^^ 13-22 0 0 13 13 1.60 2.05 078 99 EXAMPLE 13-23 8 03 30 V\ 1.74 2.05 0.85 64 CV...D, c 13-24 57 1.2 32 9 1.74 2.05 0.85 56 EXAMPLE OF 13-25 87 67 32 9 174_ 2.05 085 45 PRESENT 13-26 100 45 32 9 L74_ 2.05 0.85 37 INVENTION 13-27 100 72 32 9 174_ 2.05 085 42 13-28 100 92 32 9 1.74 2.05 0.85 57 ^"^^"V^^^^ 13-29 0 0 13 13 1.60 2.05 078 101 EXAMPLE 13-30 8 M 41 5J 1.78 2.05 087 64 cvAiini c 13-31 54 1.3 56 2.1 1.87 2.05 0.91 52 EXAMPLE __^-___^ ——^ _—— —^^—^^—- —^—^__^_— OF 13-32 78 6J 56 2J L85_ 2.05 0.90 41 PRESENT 13-33 100 38 56 27 1^ 2.05 091 32 INVENTION 13-34 100 71 56 2J L85_ 2.05 0.90 38 13-35 100 91 56 27 1.87 2.05 0.91 54 °°^J'.'^!!^^^ 13-36 0 0 13 13 1.62 2.05 079 102 EXAMPLE ______^^_ ____^__ __^_____ ^____^^__^^ __^^___^^^ _^^^ 13-37 8 02 60 2^5 1.89 2.05 0.92 63 nvAWDic 13-38 70 2.3 82 0.8 1.95 2.05 095 46 EXAMPLE OF 13-39 91 7J 82 08 1^ 2.05 0.95 40 PRESENT 13-40 100 41 82 08 1.97 2.05 0.96 26 INVENTION —^—— ——^—^—^— iiMvtNiiuiM 13-41 100 76 82 08 1.95 2.05 0.95 32 13-42 100 100 82 0.8 1.97 2.05 0.96 48 [0243] As listed in Table 30, in examples of the present invention (conditions No. 13-2 to No. 13-7, - 125 - No. 13-9 to No. 13-14, No. 13-16 to No. 13-21, No. 13-23 to No. 13-28, No. 13-30 to No. 13-35, No. 13-37 to No. 13-42), the accumulation degree of the {200} planes in the a phase was within the ranges of the present invention at the respective stages of the heat treatment. Further, as listed in Table 31, in the examples of the present invention, the alloying ratio and the ratio of the a single phase region were within the desirable ranges of the present invention. As listed in Table 31, according to the examples of the present invention, the Fe-based metal plates in which the accumulation degree of the {200} planes in the a phase was 30% or more and the accumulation degree of the {222} planes in the a phase was 30% or less were obtained. Further, in the Fe-based metal plates of the examples of the present invention, the ratio BSO/Bs was 0.85 or more. [0244] In the examples of the present invention, when the ratio of the a single phase region was 1% or more and the accumulation degree of the {200} planes was 30% or more, not only the magnetic flux density B50 but also the core loss WlO/lk maintained a higher property level. Further, it could be confirmed that the core loss WlO/lk has a still better property level when the ratio of the a single phase region is not less than 5% nor more than 80%. INDUSTRIAL APPLICABILITY [0245] The present invention is usable in, for - 126 - example, industries related to magnetic materials such as iron cores. - 127 - CLAIMS [Claim 1] A method of manufacturing an Fe-based metal plate comprising: forming a metal layer containing ferrite former on at least one surface of a base metal plate of an a-Y transforming Fe or Fe alloy; next heating the base metal plate and the metal layer to an A3 point of the Fe or the Fe alloy so as to diffuse the ferrite former into the base metal plate and form an alloy region of a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less; and next heating the base metal plate to a temperature equal to or higher than the A3 point of the Fe or the Fe alloy so as to increase the accumulation degree of the {200} planes and decrease the accumulation degree of the {222} planes while maintaining the alloy region of the ferrite phase. [Claim 2] The method of manufacturing an Fe-based metal plate according to claim 1, comprising, after the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, cooling the base metal plate to a temperature lower than the A3 point of the Fe or the Fe alloy so as to transform an unalloyed region in the base metal plate from an austenitic phase to a ferrite phase, further increase the accumulation - 128 - degree of the {200} planes and further decrease the accumulation degree of the {222} planes. [Claim 3] The method of manufacturing an Fe-based metal plate according to claim 1 or claim 2, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 30% or more and the accumulation degree of the {222} planes is decreased to 30% or less. [Claim 4] The method of manufacturing an Fe-based metal plate according to claim 1 or claim 2, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the accumulation degree of the {200} planes is increased to 50% or more and the accumulation degree of the {222} planes is decreased to 15% or less. [Claim 5] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 4, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, the ferrite former contained in the metal layer are all diffused into the base metal plate. [Claim 6] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 5, wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, - 129 - Mo, Sb, Si, Sn, Ti, V, W, and Zn. [Claim 7] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 6, wherein, in the increasing the accumulation degree of the {200} planes and the decreasing the accumulation degree of the {222} planes, an area ratio of a ferrite single phase region to the metal plate in a cross section in a thickness direction is made to 1% or more. [Claim 8] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 7, wherein as the base metal plate, used is one in which a working strain is brought about and in which dislocation density is not less than 1 x lO'"'^ m/m"^ nor more than 1 x lO'''^ m/m^. [Claim 9] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 7, wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in which rolling reduction ratio is not less than 97% nor more than 99.99%. [Claim 10] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 7, wherein as the base metal plate, used is one in which a working strain is brought about by shot blasting. [Claim 11] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 7, wherein as the base metal plate, used is one in which a working strain is brought about by cold rolling in - 130 - which rolling reduction ratio is not less than 50% nor more than 99.99% and shot blasting. [Claim 12] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 7, wherein as the base metal plate, used is one in which a shear strain of 0.2 or more is brought about by-cold rolling. [Claim 13] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 7, wherein as the base metal plate, used is one in which a shear strain of 0.1 or more is brought about by cold rolling and a working strain is brought about by shot blast ing. [Claim 14] The method of manufacturing an Fe-based metal plate according to any one of claims 1 to 13, wherein a thickness of the base metal plate is not less than 10 ]im nor more than 5 mm. [Claim 15] A Fe-based metal plate, containing ferrite former, wherein, in a surface, an accumulation degree of {200} planes in a ferrite phase is 30% or more and an accumulation degree of {222} planes in the ferrite phase is 30% or less. [Claim 16] The Fe-based metal plate according to claim 15, being formed by diffusion of the ferrite former from a surface to an inner part of an a-y transforming Fe or Fe alloy plate. [Claim 17] The Fe-based metal plate according to claim 15 or claim 16, comprising, on the surface, a metal layer containing the ferrite former. - 131 - j^Laim 18] The Fe-based metal plate according to any one of claims 15 to 17, wherein the accumulation degree of the {200} planes is 50% or more and the accumulation degree of the {222} planes is 15% or less . [Claim 19] The Fe-based metal plate according to any one of claims 15 to 18, wherein the ferrite former are at least one kind selected from a group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn. [Claim 20] The Fe-based metal plate according to any one of claims 15 to 19, comprising a 1% ferrite single phase region or more in terms of an area ratio in a thicknesswise cross section of the metal plate. Dated this 02/05/2012 ("^^"^^'^llfe^ ATTORNEY FOR THE APPLICAfr[S] - 132 -