Method of producing grain-oriented silicon steel sheets having excellent magnetic properties

Abstract: A grain-oriented silicon steel sheet having excellent magnetic properties can be stably produced by adjusting properly the C content in a silicon steel to be used as a starting material depending upon the Si content in the steel, removing a proper amount of C from the steel during the course after the hot rolling and before the final cold rolling, and further carrying out the final cold rolling at a reduction rate of 40-80%.

Description: The present invention relates to a method of producing grain-oriented silicon steel sheets having excellent magnetic properties. Grain-oriented silicon steel sheets are mainly used in the iron cores of transformers and other electric instruments. and are required to have excellent magnetic properties. that is, to have an excellent magnetizing property and a low iron loss. Recently. techniques for producing silicon steel sheets; have progressed; and a grain-oriented silicon steel sheet having an excellent magnetizing property, that is, having a high magnetic induction i.e. a B₁₀ value of more than 1.89 T (teslas) has been obtained and contributes to the production of small size transformers and other electric instruments and to a decrease in noise; and further there has been obtained a grain-oriented silicon steel sheet having a low iron loss of W 17/50 ≦1.10 W/kg in a sheet thickness of 0.30 mm, that is, having an iron loss of not more than 1.10 W per kg of the steel sheet when the steel sheet has a thickness of 0.30 mm and is magnetized under a magnetic induction of 1.7 T and at a frequency of 50 Hz. A fundamental requirement for obtaining grain-oriented silicon steel sheets having such excellent magnetic properties is that secondary recrystallized grains having (110)[001] orientation are fully developed during the final annealing. It is commonly known that the following conditions are required for this purpose, that is, the presence of inhibitor which suppresses strongly the growth of primary recrystallized grains having an undesirable orientation other than the (110)[001] orientation during the secondary recrystallization, and the formation of a recrystallization texture which is effective for the predominant and sufficient development of secondary recrystallized grains having a strong (110)[001] orientation. As the inhibitors, there are generally used fine precipitates of MnS, MnSe, AIN and the like. Further, grain boundary segregation elements, such as Sb, As, Bi, Pb. Sn and the like, are occasionally used together with an inhibitor to enhance its effect. In order to form the effective recrystallization texture, a method wherein the hot rolling condition and the cold rolling condition are properly combined, is carried out, and a complicated step which consists of two cold rollings with an intermediate annealing between them. is carried out for this purpose. Hitherto, slabs to be used as a starting material for the production of grain-oriented silicon steel sheets have been produced from molten steel through ingot making and slabbing. Recently however slabs have been produced directly from molten steel by the continuous casting. Defects in the crystal texture and recrystallization texture due to the use of continuously cast slabs causes troubles in the grain-oriented silicon steel sheet produced therefrom. That is, when it is intended to obtain fine precipitates of MnS, MnSe, AIN and the like, which are effective as inhibitors, it is necessary that the slab is heated at a high temperature of not lower than 1,250°C for a long period of time before the hot rolling to dissociate and to solid solve fully the inhibitor element into the steel. and the cooling step on hot rolling is controlled to precipitate the inhibitor element having a proper fine size. However, in the continuously cast slab, extraordinarily coarse crystal grains are apt to develop during the high temperature heating of the slab as described above, and incompletely developed secondary recrystallized texture, called fine grain streaks is formed in the resulting silicon steel sheet product due to the extraordinarily coarse crystal grains, and the silicon steel sheet product is poor in magnetic properties. There have hitherto been proposed several methods in order to prevent the formation of the above-described fine grain streaks and to improve the magnetic properties. For example, Japanese Patent Laid-Open Application No. 119,126/80 discloses a method, wherein a slab is subjected to a recrystallization rolling when the slab is hot rolled into a given thickness, that is, the texture of the slab just before the recrystallization rolling is controlled such that the α-phase matrix contains at least 3% of precipitated γ-phase iron, and the slab is subjected to a recrystallization rolling at a high reduction rate of not less than 30% per one pass within the temperature range of 1,230-960°C. The inventors have proposed in Japanese Patent Application No. 31,510/81 a method, wherein a slab is mixed with the necessary amount of C depending upon the Si content, and not less than a given amount of γ-phase iron is formed within a specifically limited temperature range during the hot rolling, whereby coarse crystai grains developed in the slab during the heating at high temperature are broken to prevent effectively the formation of fine grain streaks in the product. However, according to the above described method of forming not less than a given amount of γ-phase iron in the slab during its hot rolling. although formation of fine grain streaks in the product can be prevented, the desired magnetic properties can not always be obtained, and moreover the prevention of the formation of fine grain streaks is very unstable. Also fine grain texture may be formed all over the product which deteriorates noticeably its magnetic properties. Therefore, this method is still insufficient to produce a stable effect. which is a most important factor in the commercial production of grain-oriented silicon steel sheet. The object of the present invention is to obviate the drawbacks of the above described conventional techniques in the production of grain-oriented silicon steel sheets and to provide a method which can always stably produce steel sheets having excellent magnetic properties. According to the present invention there is provided a method of producing a grain-oriented silicon steel sheet having excellent magnetic properties from a continuously cast slab, comprising the steps of (i) forming a hot rolled steel sheet by hot rolling a continuously cast slab of silicon steel consisting of from 2.8 to 4.0% by weight of Si, 0.02 to 0.15% by weight of Mn, 0.008-0.080% by weight in total of at least one of S and Se, and C within the range defined by the following formula 0.37[Si%]+0.27≦log([C%]×10³)≦0.37[Si%]+0.57 wherein [Si%] and [C%] represent the contents (% by weight) of Si and C in the silicon steel, respectively, with the balance being Fe, incidental impurities and optionally grain boundary elements; (ii) coiling the hot rolled steel sheet; (iii) subjecting the coiled steel sheet to two or more cold rollings with an intermediate annealing between them and using a reduction rate of from 40 to 80% in the final cold rolling to produce a finally cold rolled steel sheet having a final gauge; and (iv) subjecting the finally cold rolled steel sheet to decarburization annealing and final annealing; the method including the step of removing 0.006-0.020% by weight of C from the steel after the completion of the above described hot rolling step and before the beginning of the above described final cold rolling. US-A-4 123 298 discloses the production of grain oriented silicon steel sheets having improved magnetic properties by a method which comprises the steps of hot rolling a slab to form a hot rolled sheet: continuously annealing, quenching and cooling the sheet; descaling and pickling the sheet; cold rolling the sheet in one or more stages to final gauge, the final cold reduction being from about 65% to about 95%; continuously decarburizing the cold rolled sheet; subjecting the decarburised sheet to continuous strip annealing; providing the sheet with an annealing separator; and subjecting the sheet to final box annealing. However there is no suggestion that the C content of the silicon steel starting material should be selected in dependence on the Si content or that steps should be taken to remove specific amounts of C prior to the final cold rolling as required in accordance with the present invention. EP-A-00 47 129 describes the production of grain oriented silicon steel sheets having improved magnetic properties by forming a hot rolled sheet; cold rolling the hot rolled sheet; carrying out an intermediate annealing; subjecting the annealed sheet to a final cold rolling to final gauge; decarburizing the cold rolled sheet; and subjecting the decarburised sheet to final annealing. The carbon content of the steel sheet is adjusted so that prior to the final cold rolling it is from 0.020 to 0.060%. However, there is no suggestion that this adjustment should be carried out by removing specific amounts of C after the hot rolling step. Further there is no suggestion that the C content of the silicon steel starting material should be selected in dependence on the Si content. For a better understanding of the present invention and to show how the same may be carried out, reference will now be made, by way of example, to the accompanying drawings, in which:- Figure 1 is a graph illustrating the influences of the Si content and C content of a slab used as a starting material for a grain-oriented silicon steel sheet upon the iron loss value of the sheet; Figure 2A is a microphotograph illustrating the fine grain streaks in a grain-oriented silicon steel when the amount (estimated value) of γ-phase iron formed at 1,150°C during the hot rolling of the slab is smaller than the lower limit of the proper range of 10-30%; Figure 2B is a microphotograph illustrating a grain-oriented silicon steel sheet having a heterogeneous texture, which consists of a mixture of fine grains and normally developed secondary recrystallized grains, and which is formed in the case where the amount (estimated value) of γ-phase iron formed during the hot rolling of a slab at 1,150°C is somewhat larger than the upper limit of the proper range of 10-30%; Figure 3A is a graph illustrating the relationship between the decarburized amount ΔC after hot rolling and before final cold rolling during production of a grain-oriented silicon steel sheet and the magnetic induction B₁₀ of the sheet; Figure 3B is a graph illustrating the relationship between the amount ΔC decarburized after hot rolling and before final cold rolling during the production of a grain oriented sheet and the iron loss value W 17/50 of the sheet; Figure 4A is a microphotograph illustrating the primarily recrystallized texture of a steel before final cold rolling in the case where the decarburized amount ΔC is 0.005% or less and is thus less than the amount ΔC to be decarburized (0.006-0.020%) in accordance with one of the requirements of the present invention; Figure 4B is a microphotograph illustrating the primarily recrystallized texture of a steel before the final cold rolling in the case where the decarburized amount ΔC is nearly equal to 0.010% and is proper in accordance with the present invention: Figure 4C is a microphotograph illustrating the primarily recrystallized texture of a steel before the final cold rolling in the case where the decarburized amount ΔC is 0.021% or more and is in excess of that required in accordance with the present invention; Figures 5A, 5B and 5C are {200} pole figures of the steels having the primarily recrystallized textures shown in Figures 4A. 48 and 4C, respectively; and Figures 6A, 6B and 6C are microphotographs illustrating the crystal textures of silicon steel sheets produced from the steels having the primarily recrystallized textures shown in Figures 4A and 5A; 4B and 5B; and 4C and 5C, respectively. The inventors have investigated the cause imparting unstable magnetic properties to grain-oriented silicon steel sheets in the above described conventional methods, and have found out the following facts. That is, the γ-phase iron formed in the slab used as starting material during its hot rolling acts harmfully on the fine precipitates of MnS, MnSe and the like, which act as inhibitors and particularly the formation of an excessively large amount of γ-phase iron deteriorates greatly the ability of the inhibitor to allow a sufficient development of secondary recrystallized grains. Further, even when a proper amount of γ-phase iron is formed, the γ-phase iron acts harmfully on the formation of a proper crystal texture and recrystallization texture during the cold rolling step after the γ-phase iron has been utilized for dividing coarse crystal grains into small grain size during the hot rolling. The inventors have variously investigated how to overcome these harmful functions and have found a novel method of doing so. As a result, the present invention has been accomplished. The present invention will be explained referring to basic experimental data for the present invention. Figure 1 invention the relation between the Si and C content of a slab used as a starting material and the iron loss W 17/50 of the resulting grain-oriented silicon steel sheet in the following experiment. A large number of slabs, which contained 0.015-0.035% (in this specification, "%" relating to the amount of a component of the steel means "% by weight") of Se and 0.03-0.09% of Mn as an inhibitor, Si in an amount within each of three groups of 2.8-3.1%, 3.3-3.5% and 3.6-3.8%, and C in various amounts within the range of 0.01-0.10%, were produced from ingots, and each slab was heated at 1,400°C for 1 hour and then hot rolled to produce a hot rolled sheet having a thickness of 2.5 mm. Each hot rolled sheet was subjected to two cold rollings with an intermediate annealing between them to produce a finally cold rolled sheet having a final gauge of 0.30 mm. Each finally cold rolled sheet was subjected to a decarburization annealing and a final annealing to obtain a final product in the form of a grain-oriented silicon steel sheet. In the above described experiment, the atmosphere during the intermediate annealing was variously changed from a decarburizing atmosphere to a non-decarburizing atmosphere, and the final cold rolling reduction rate was set within the range of 50-70%. The broken lines A, B, C, D and E described in Figure 1 represent an estimated value, calculated from the following formula (1), of the amount of γ-phase iron formed at 1,150°C in the slab during the hot rolling, and represent 40, 30, 20, 10 and 0%, respectively, of the estimated amount of the γ-phase iron formed. In general, the amount of γ-phase iron formed varies depending upon the Si and C contents in the slab and the heating temperature thereof. The following formula (1) was deduced from the measured values of the Si and C contents in a steel and the measured value of the amount of γ-phase iron formed in the steel under equilibrium conditions at 1,150°C with respect to sample silicon steels containing various amounts of Si and C. γ%=67 log([C%]×10³)-25[Si%]-8. In formula (1), the value in the brackets [ ] represents the % by weight of C and Si in the steel. The measured values of the iron loss W 17/50 of the resulting steel sheets formed from the three groups of steels as classified by the Si content are shown in the following Table 1 and Figure 1. It can be seen from Table 1 that, although there is a difference in the estimated iron loss value of the three groups of steels, steels capable of giving a low iron loss value (W 17/50 ) to the resulting grain-oriented silicon steel sheets are present between broken lines B and D shown in Figure 1. The amount of γ-phase iron formed during the hot rolling of these is within the range of 10-30% independently of the Si content. However, the γ-phase iron formed during the hot rolling is not present under equilibrium conditions but is present under a metastable condition, and it is difficult to determine accurately the amount of γ-phase iron formed at 1,150°C during the actual hot rolling. Accordingly, limiting the C content in a steel, which gives low iron loss to the steel sheet product, in accordance with the amount of γ-phase iron formed is not appropriate for practical operation. It is more appropriate for practical operation to limit the range of the C content in a steel, which range satisfies the range of 10-30% of the amount of γ-phase iron formed as given by the above described formula (1), in dependence on the Si content. Based on this idea, the proper range for the C content in a silicon steel used as a starting material for imparting a low iron loss to the resulting grain-oriented silicon steel sheet, which C content varies depending upon the Si content in the steel, is given by the following formula (2) 0.37[Si%]+0.27≦log([C%]×10³)≦0.37[Si]+0.57. This is a first requirement to be satisfied in accordance with the present invention. That is, when the C content in the starting steel is lower than the lower limit of the proper range for the C content as defined by the formula (2) depending upon the Si content (that is, when a starting steel has a composition which forms less than 10% of γ-phase iron during the hot rolling), the product has distinct fine grain streaks as illustrated in Figure 2A, and has poor magnetic properties. While, when a starting steel has a composition which forms 10% (shown by the line D in Figure 1) or more of γ-phase iron, the product has substantially no fine grain streaks and consists mainly of normally developed secondary recrystallized grains. Accordingly, in order that coarse crystal grains developed extraordinarily during the heating of a slab at high temperature are divided into small size grains and broken during the hot rolling and that the development of fine grain streaks is prevented, it is necessary to form not less than a given amount of γ-phase iron. It has been found out that this given amount of γ-phase iron can be formed by ensuring that C is in the slab in such an amount that not less than 10% of γ-phase iron is formed, depending upon the Si content, during the hot rolling of the slab when the slab is kept under equilibrium conditions. When a slab contains an excessively large amount of C (that is, when the slab has a composition which forms more than 30% of γ-phase iron during the hot rolling), the product has a crystal texture which is wholly occupied by fine grains consisting of incompletely developed secondary recrystallized grains, and has very poor magnetic properties. When the excess amount of C approaches the upper limit of the range of the proper C content determined depending upon the Si content, the crystal texture of the product varies and represents a so-called heterogeneous texture consisting of a mixture of fine grains and normally developed secondary recrystallized grains as illustrated in Figure 2B. In this case the magnetic properties are somewhat improved but are still insufficient. The reason why the development of secondary recrystallized grains is disturbed by the excess amount of C beyond the upper limit of the proper range for the C content represented by the above described formula (2) is not clear, but is probably as follows. That is, due to the lowering of temperature of the slab during its hot rolling following the high temperature heating thereof, the amount of C solid solved in the α-phase iron is decreased to form in the steel the γ-phase iron having a high C content, and the amount of the γ-phase iron increases until the maximum amount of γ-phase iron is formed at about 1,150°C. This γ-phase iron has a very high C content of not less than about 0.2%, which is higher than the C content in the α-phase iron. S and Se, which have been formed by dissociation of inhibitor and which are solid solved in the α-phase iron during the high temperature heating of the slab, are difficultly soluble in the γ-phase iron. Accordingly, it can be assumed that S and Se are precipitated and grow into coarse grains during the initial high temperature stage of hot rolling and lose their effect as inhibitors. Based on the above described mechanism, when γ-phase iron formed during the hot rolling of a slab exceeds a certain value, the proportion, in the total sheet of regions which are not suitable for the presence of an inhibitor, increases and causes incomplete development of secondary recrystallized grains, and a product having excellent magnetic properties can not be obtained. As a result, the inventors have found out the following fact. Only when the silicon steel to be used in the present invention contains C and Si in such amounts that can form 10-30% of γ-phase iron under equilibrium conditions during the hot rolling, can the object of the present invention be attained, and it is very effective in order to obtain a product having excellent magnetic properties if the silicon steel has a C content defined by the above described formula (2) depending upon the Si content. However, even when the amount of γ-phase iron formed is within the range of 10-30%, some of the resulting grain-oriented silicon steel sheets do not have a satisfactorily low iron loss (see Figure 1) and the limitation of the Si and C contents in accordance with formula (2) is still insufficient to produce silicon steel sheets having stable magnetic properties on a commercial scale. The inventors have made various investigations in order to obviate this drawback, and have formed out that it is very effective to remove 0.006-0.020% of C from the steel after completion of the hot rolling and before completion of the intermediate annealing carried out before the final cold rolling in order to obtain stably a product having excellent magnetic properties. This is a second requirement to be satisfied in accordance with the present invention. This second requirement has been ascertained by the inventors from the following experiment. That is, grain-oriented silicon steel sheets were produced from slabs having a composition which had an Si content within each of the two groups of 2.8-3.1% and 3.3-3.5% shown in Figure 1 and had a C content (dependent upon the Si content) that corresponded to 10-30% of the amount of γ-phase iron formed at 1,150°C during the hot rolling of the slab. The relationship between the magnetic properties of the products and the difference in the C content between the hot rolled sheet and the intermediately annealed sheet before final cold rolling (that is, the relationship between the magnetic properties and the decarburized amount (ΔC)) were investigated. Figures 3A and 3B show the results. Figures 3A and 38 are graphs illustrating the relationship between the amount decarburized during the process (which decarburization is carried out after the hot rolling and before the final cold rolling), and the magnetic induction B₁₀(T) and the iron loss W 17/50 , respectively, in a large number of sample steels having a Si content in the range of 2.8-3.1% shown by white circles or having a Si content in the range of 3.3-3.5% shown by black circles in Figures 3A and 3B. It can be seen from Figures 3A and 3B that, when the decarburized amount ΔC is not less than 0.006% and not more than 0.020%, the excellent magnetic properties desired in the present invention can be stably obtained. When the ΔC is less than 0.006% or more than 0.020%, the magnetic induction is low and the iron loss is relatively large, and these values are inadequate magnetic properties in accordance with the present invention. The amount decarburized during the process after the hot rolling and before the final cold rolling in an ordinary operation is generally 0.005% or less. Therefore, in order to achieve a decarburized amount of 0.006-0.020%, which has been found out to be an effective amount in the present invention, the treatments carried out during the process after the hot rolling and before the final cold rolling must be carried out under particularly limited conditions. In the case where the magnetic properties have not been satisfactorily improved by the above described first requirement of the present invention, they can be satisfactorily improved by this second requirement of the present invention, wherein a decarburization is forcedly carried out during the process after the hot rolling and before the final cold rolling. In this way excellent magnetic properties can be stably obtained. The inventors have carried out the following experiment in order to investigate the reason why the above described removal of a proper amount of C during the process after the hot rolling and before the final cold rolling is effective in improving magnetic properties. That is, the sample steels used in the experiment shown in Figures 3A and 3B were classified into the following three groups corresponding to the decarburized amount. (A) Decarburized amount is short: ΔC=≦0.005% (B) Decarburized amount is proper: ΔC≅0.010% (C) Decarburized amount is excess: ΔC≧0.021%. Figures 4A, 4B and 4C illustrate the primarily recrystallized textures, after the intermediate annealing before the final cold rolling, of the above described sample steels (A), (B) and (C), respectively; Figures 5A, 58 and 5C are {200} pole figures illustrating the primarily recrystallized recrystallization texture of the sample steels (A), (B) and (C), respectively; and Figures 6A, 6B and 6C are microphotographs illustrating the crystal texture of the products in the above described sample steels (A), (B) and (C), respectively. It can be seen from Figures 4A through 6C that, in the sample steel (A) wherein the decarburized amount is short, the primarily recrystallized texture before the final cold rolling has not a uniform crystal grain size. Fine grains are formed into massive grains and are distributed in the texture as illustrated in Figure 4A. Further the recrystallization texture is an unfavorable microstructure, wherein the intensity of secondary recrystallized grains having a (110)[001] orientation is low and crystal grains having a relatively strong {111}<1 12 > orientation are dispersed as illustrated in Figure 5A. As a result, the crystal texture of the product is a mixed texture formed of fine grains and incompletely developed secondary recrystallized grains as illustrated in Figure 6A. In the sample steel (B), wherein the decarburized amount is proper, the crystal grain size before the final cold rolling is uniform the proper as illustrated in Figure 4B, and the recrystallization texture is a favorable texture wherein the intensity of secondary recrystallized grains having a (110)[001] orientation is high as illustrated in Figure 5B. Moreover, the crystal texture of the product is formed of normally and fully developed secondary recrystallized grains as illustrated in Figure 6B. In the sample steel (C), wherein the decarburized amount is in excess, the crystal grain size before the final cold rolling is not uniform and coarse crystal grains are dispersed as illustrated in Figure 4C, and the recrystallization texture is unfavorable due to the development of a small amount of recrystallized grains having a (110)[001] orientation as illustrated in Figure 5C. Therefore, the crystal texture of the product resulting from such recrystallization texture is occupied by extraordinarily coarse secondary recrystallized grains as illustrated in Figure 6C. Many of these secondary recrystallized grains have orientations somewhat deviated from the (110)[001] orientation, and the product has insufficient magnetic properties. As described above, it has been found that the γ-phase iron, which has acted effectively on the slab in the hot rolling step to divide and break coarse grains contained in the slab, is dispersed in the slab in the form of coarse massive carbide during the cold rolling step, and a non-uniform crystal texture and unfavorable recrystallization texture are formed around the coarse massive carbide. According to the present invention, the above described massive carbide is eliminated by the removal of a proper amount of carbon, whereby a favorable crystal texture and recrystallization texture can be obtained. However, when the decarburized amount is short or excess, the crystal texture obtained is not uniform and is not favorable, and a recrystallization texture having an intense (110)[001] orientation as required in accordance with the present invention can not be obtained. The inventors have ascertained the following fact in the further investigation. The amount of C necessary for forming γ-phase iron during the hot rolling step is larger than the proper amount of C for the cold rolling step and is detrimental in obtaining the desired product having excellent magnetic properties. In order to obviate this drawback, it is necessary that 0.006-0.020% of C is removed from the steel which has originally contained C in the amount necessary for forming γ-phase iron. Now, an explanation will be made with respect to the limitation of the composition of the silicon steel to be used in the present invention. Si: When the Si content is lower than 2.8%, the sufficiently low iron loss value desired in the present invention can not be obtained. While, when the Si content is higher than 4.0%, the steel is brittle, has poor cold rollability, and is difficult to cold roll using conventional commercial rolling operations. Therefore, the Si content is limited within the range of 2.8-4.0%. As the Si content is increased within this range of 2.8-4.0%, products having a low iron loss can be generally obtained. In practical operations, the use of a steel having a high Si content is expensive due to Si and further decreases the yield on cold rolling, and this results in a very expensive product. Therefore, the Si content should be properly selected depending upon the desired level of iron loss. C: It has been already explained as the first requirement of the present invention that the C content must be adjusted to the range defined by the above described formula 2 depending upon the Si content. That is, it is necessary that the C content is limited to the range which corresponds substantially to 10-30% of the amount of γ-phase iron to be formed at 1,150°C during the hot rolling as illustrated in Figure 1. Concrete values for the Si content and C content are shown in the following Table 2. However, when the C content exceeds 0.1%, a long time is required for the decarburization step, and this is expensive. Therefore, it is desirable that the necessary amount of C is selected to be not larger than 0.1%. Mn, S and Se: Mn, S and Se are added to steel as inhibitors and are necessary elements in order to suppress the development of primarily recrystallized grains during the final annealing and to develop secondary recrystallized grains predominantly having a (110)[001] orientation. However, when the amount of Mn is outside the range of 0.02-0.15% or the total amount of at least one of S and Se is outside the range of 0.008-0.08%, the development of secondary recrystallized grains is unstable, and the excellent magnetic properties desired in the present invention can not be obtained. Therefore, the contents of Mn, S and Se should be limited within the above described ranges. The composition of the silicon steel to be used in the present invention consists essentially of the above described elements with the remainder being substantially Fe and impurities. The steel may occasionally contain incidental elements such as grain boundary segregation type elements, for example Sb, As, Bi, Pb, Sn and the like either alone or in admixture to promote the effect of the inhibitor. In the present invention, the use of grain boundary segregation type elements does not deteriorate the magnetic properties of the steel sheet product. Now, an explanation will be made with respect to the reason why the rolling condition is limited in the present invention. In accordance with the present invention, a silicon steel slab having the above described composition is heated to a high temperature, generally not lower than 1,250°C, hot rolled by a commonly known method to produce a hot rolled steel sheet having a thickness of for example 1.2-5.0 mm, and then coiled. The coiled steel sheet is subjected to two or more cold rollings with an intermediate annealing between them, wherein the final cold rolling is carried out at a reduction rate of 40-80%, to produce a finally cold rolled sheet having a final gauge, e.g. of 0.15-0.50 mm. The intermediate annealing is carried out at a temperature within the range of 750-1,100°C. In general, two or more cold rollings with an intermediate annealing between them are carried out to produce a finally cold rolled sheet having the final gauge. The reason why the final cold rolling reduction rate is limited to 40-80% is as follows. In the present invention, a proper amount of C is removed from the steel during the course of the cold rolling to make the crystal texture uniform and to promote the development of secondary recrystallized grains having a (110)[001] orientation in the recrystallization texture. This effect can not be attained with a reduction rate of less than 40% or more than 80% on final cold rolling. It can be attained only when the final cold rolling reduction rate is within the range of 40-80%. The resulting finally cold rolled sheet is subjected to a decarburization annealing and then to a final annealing to obtain a product. The slab to be used as a starting material in the present invention is a slab produced by a continuous casting method. The slab is heated to a high temperature of not lower than 1,250°C, subjected to hot rolling by a commonly known method to produce a hot rolled steel sheet having a thickness of for example 1.2-5.0 mm. and then coiled. When a decarburization treatment is carried out without carrying out the normalizing annealing, a product having magnetic properties superior to those obtained by conventional methods can be obtained. That is, this process has the merit that the production steps are simple and the merit that the magnetic properties are excellent. It is however advantageous. in the present invention, that the decarburization treatment is carried out and further that the normalizing annealing is carried out. In this case. a product can be obtained having magnetic properties superior to those obtained by the above described process wherein no normalizing annealing is carried out. The above obtained coiled sheet, directly or after being subjected to a normalizing annealing, is subjected to two or more cold rollings with an intermediate annealing between them at a temperature of 750-1,100°C to obtain a finally cold rolled sheet having a final gauge of for example 0.15-0.50 mm. During the above described steps, 0.006-0.020% of C is removed from the steel after the hot rolling and before the final cold rolling. For the decarburization treatment, there can be used a method wherein the hot rolled sheet is applied with Fe₂O₃ or other oxide and coiled and the decarburization is promoted by utilizing self-annealing. Alternatively the hot rolled sheet may be coiled and immediately placed in a box kept under a decarburizing atmosphere to promote the decarburization. Further, the decarburization treatment can be carried out during at least one of the above described normalizing annealing and intermediate annealing steps. A decarburization treatment during the normalizing-annealing step or the intermediate annealing step can be easily carried out by adjusting properly the atmosphere of the commonly known continuous annealing furnace. The strength of the decarburizing ability of the annealing atmosphere during the decarburization should-be properly adjusted depending upon the composition of the starting slab, the sheet thickness, the annealing time and the like. Among the above described decarburization treatments, decarburization during the intermediate annealing step is most advantageous because the decarburizing amount can be easily adjusted and is uniform due to the small sheet thickness. Further the ordinary annealing atmosphere can be easily made into a decarburizing atmosphere, whereby the object of the present invention can be easily attained and the installation and production costs are low. The above described hot rolled sheet is cold rolled as described above. In this cold rolling, the final cold rolling is carried out at a reduction rate of 40-80% to promote the formation of a uniform crystal texture and the development of secondary recrystallized grains having a (110)[001] orientation in the recrystallization texture. The finally cold rolled sheet, which has a C content lower by 0.006-0.020% than the amount of C contained in the starting slab, is further subjected to a decarburization annealing for example at a temperature within the range of 750-850°C under a wet hydrogen atmosphere to decrease fully the C content to for example not more than 0.003%. Then, an annealing separator, such as MgO or the like, is applied to the decarburized sheet, and the above treated sheet is subjected to a final annealing. The final annealing is carried out in order to develop fully secondary recrystallized grains having a (110)[001] orientation and at the same time to remove S and Se, which have previously added to the slab as an inhibitor, and other impurity elements, such as N and the like, and to purify the sheet. The final annealing is generally carried out at a high temperature not lower than 1.000°C. However, it is most preferable to carry out the final annealing according to a method disclosed by the inventors in U.S. Patent No. 3,932,234, wherein the sheet to which an annealing separator has been applied is kept at a temperature within the range of 820-920°C. which develops secondary recrystallized grains. for at least about 10 hours to develop fully secondary recrystallized grains, and successively subjected to a purification annealing at a temperature not low than 1,000°C in order to remove the impurities. Grain-oriented silicon steel sheets having excellent magnetic properties can be stably produced through the above described treating steps of the present invention. The following Examples are given for the purpose of illustrating this invention and are not intended as limitations thereof. Example 1 Molten steels having compositions which contained 3.15% of Si and three levels of 0.021, 0.045 or 0.072% of C, and further contained 0.07% of Mn. 0.03% of Se and 0.03% of Sb as inhibitor; or compositions which contained 3.60% of Si and three levels of 0.033, 0.058 or 0.094% of C, and further contained 0.07% of Mn, 0.03% of Se and 0.03% of Sb as inhibitor, were continuously cast into two or three slabs, each having a thickness of 200 mm. Each slab was heated at 1,380°C for 1 hour, hot rolled into a thickness of 2.5 mm, and then coiled. The hot rolled and coiled sheets were annealed at 980°C for 30 seconds, and then cold rolled into a thickness of 0.75 mm. Successively. the sheets were subjected to a continuous intermediate annealing at 950°C for 2 minutes under an atmosphere of P H 2 O /P H2 =0.003-0.35 by a commonly known method so as to remove 0.002-0.030% (decarburized amount ΔC) of carbon, and then finally cold rolled at a reduction rate of 60% into a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing at 800°C in wet hydrogen, treated with an annealing separator consisting mainly of MgO, subjected to a final annealing at 1,200°C for 10 hours, and then an insulating coating was applied to produce a grain-oriented silicon steel sheet. The magnetic properties of the products are shown in the following Table 3. In Table 3, the value in the parentheses under the heading of C content in the slab indicates the amount (estimated value) of γ-phase iron formed in the steel at 1,150°C during the hot rolling. It can be seen from Table 3 that, in comparative steels of sample Nos. 1, 2, 6, 7, 8, 9, 13, 14 and 15, which do not satisfy any one of the requirements of the present invention, the iron loss value is high and the magnetic induction is low. That is, in sample steel Nos. 1, 2, 8 and 9, the C content in the slab is lower than the lower limit of the range defined in the present invention, and the amount of γ-phase iron formed is smaller than the lower limit of the proper range of 10-30% as required by the present invention, and accordingly fine grain streaks are formed as illustrated in Figure 2A. While, in sample steel Nos. 6, 7, 13, 14 and 15, the C content in the slab is higher than the upper limit of the range defined in the present invention, and the amount of γ-phase iron formed is larger than the upper limit of the proper range of 10-30% as required by the present invention. Accordingly the crystal texture consists of a mixture of fine grains and normally developed secondary recrystallized grains as illustrated in Figure 2B, and the products have a high iron loss value and a low magnetic induction. Further, in sample steel Nos. 2, 6 and 9, the product has a slightly improved magnetic induction because the decarburized amount ΔC is within the range of 0.006-0.020% defined in the present invention, but the product has not satisfactorily improved magnetic properties because the C content in the slab does not satisfy the requirement defined in the present invention. Further, even when the amount of γ-phase iron formed is within the proper range of 10-30% as required by the invention and at the same time the C content in the slab satisfies the above described formula (2) as defined in the present invention, if the decarburized amount ΔC is not within the range of 0.006-0.020% as defined in the present invention, a product having a satisfactorily low iron loss value and a satisfactorily high magnetic induction can not be obtained as is illustrated in sample steel Nos. 3, 5, 10 and 12. On the contrary, in sample steel Nos. 4 and 11, which satisfy all the requirements defined by the present invention, the product has a satisfactorily low iron loss value and at the same time a satisfactorily high magnetic induction. Also it has a fully developed secondary recrystallized texture as illustrated in Figure 6B, and proves clearly the effect of the present invention. Example 2 Three slabs containing 3.35% of Si, 0.050% of C, 0.05% of Mn and 0.015% of S and having a thickness of 200 mm were heated at 1,350°C for 1 hour, hot rolled into a thickness of 2.0 mm and then coiled. These hot rolled and coiled sheets were annealed hot 1,000°C for 30 seconds, cold rolled into a thickness of 0.75 mm, subjected to a continuous intermediate annealing at 950°C for 2 minutes under an atmosphere of P H 2 O /P H 2 =0.003-0.35 by a commonly known method so as to remove 0.002%, 0.013% or 0.025% (decarburized amount ΔC) of carbon, and then finally cold rolled into a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing at 800°C in wet hydrogen, treated with an annealing separator consisting mainly of MgO, subjected to a final annealing at 1,200°C for 10 hours, and then provided with an insulating coating to obtain grain-oriented silicon steel sheets. The magnetic properties of the products are shown in the following Table 4. It can be seen from Table 4 that, in sample steel No. 17, whose decarburized amount ΔC is 0.002%, (which is less than the lower limit of the range defined in the present invention), the texture of the resulting steel sheet contains 30% of fine grains. Thus a large amount of fine grains is developed, and a satisfactorily low iron loss value can not be obtained although the amount (estimated value) of γ-phase iron formed is within the proper range of 10-30%. Further, in sample steel No. 19, whose decarburized amount ΔC is excessively large (0.025%), the texture of the resulting steel sheet contains no fine grains, but the secondary recrystallized grains are coarse. As a result, the sheet of sample steel No. 19 has a satisfactorily high magnetic induction, but has not a satisfactorily low iron loss value. On the contrary, in sample steel No. 18 which satisfies all the requirements defined in the present invention, the resulting steel sheet has a low iron loss value and at the same time has a high magnetic induction. Therefore, according to the present invention, a satisfactory grain-oriented silicon steel sheet can be obtained. Example 3 Three continuously cast slabs of 200 mm thickness and having a composition containing 3.0% of Si, 0.040% of C, 0.07% of Mn and 0.03% of Se were heated at 1,320°C for 1 hour, hot rolled into a thickness of 3.0 mm, and then coiled. The hot rolled and coiled sheets were subjected to a normalizing annealing at 980°C for 30 seconds and then cold rolled into a thickness of 0.80 mm, successively subjected to an intermediate annealing at 950°C for 2 minutes under an atmosphere of PH₂O/PH₂=0.003-0.35 by a commonly known method so as to remove 0.003%, 0.012% or 0.024% (decarburized amount ΔC) of carbon, and then finally cold rolled into a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing, and then to a final annealing at 1,200°C for 10 hours. The finally annealed sheets were provided with an insulating coating to obtain grain-oriented silicon steel sheets. The magnetic properties of the products are shown in the following Table 5. It can be seen from Table 5 that, in sample steel No. 20, whose decarburized amount ΔC is less than the lower limit of the range of 0.006-0.020% defined in the present invention, the texture of the resulting steel sheet contains 15% of fine grains, and a low iron loss value can not be obtained. Moreover the magnetic induction is low. In sample steel No. 22, the decarburized amount ΔC is 0.024% (which is more than the upper limit of the above described range) and although the texture of the resulting steel sheet does not contain fine grains, a sufficiently low iron loss value can not be obtained. On the contrary, in sample steel No. 21, whose decarburized amount is within the range defined in the present invention and which satisfies the other requirements, the resulting steel sheet has a satisfactorily low iron loss value and a very high magnetic induction. Example 4 Three continuously cast slabs of 200 mm thickness and having a composition containing 3.0% of Si, 0.040% of C, 0.07% of Mn and 0.025% of S were heated at 1,320°C for 1 hour, hot rolled into a thickness of 3.0 mm, and then coiled. The hot rolled and coiled sheets were pickled, cold rolled into a thickness of 0.8 mm, successively subjected to an intermediate annealing at 900°C for 5 minutes under an atmosphere of P H2O /P H2 =0.003-0.35 by a commonly known method so as to remove 0.003%, 0.012% or 0.024% (decarburized amount ΔC) of carbon, and then finally cold rolled into a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing, and then to a final annealing at 1,200°C for 10 hours. The finally annealed sheets were provided with an insulating coating to obtain grain-oriented silicon steel sheets. The magnetic properties of the products are shown in the following Table 6. It can be seen from Table 6 that, in sample steel No. 23, whose decarburized amount ΔC is less than the lower limit of the range of 0.006-0.020% defined in the present invention, the texture of the resulting steel sheet contains 25% of fine grains, a low iron loss value can not be obtained, and moreover the magnetic induction is low; while, in sample steel No. 25, whose decarburized amount ΔC is 0.024% (which is more than the upper limit of the above described range) although the texture of the resulting steel sheet does not contain fine grains, a sufficiently low iron loss value can not be obtained. On the contrary, in sample steel No. 24, whose decarburized amount is within the range defined in the present invention and which satisfies the other requirements, the resulting steel sheet has a satisfactorily low iron loss value and a very high magnetic induction. In a conventional method, wherein a normalizing annealing is carried out, the resulting steel sheet generally has magnetic properties of about W 17/50 =1.19-1.26 and B₁₀=1.83-1.86. While, according to the present invention, a steel sheet having magnetic properties, which are superior to those of the above described steel sheet produced by carrying out a normalizing annealing in a conventional method, can be obtained even when a normalizing annealing is not carried out as is illustrated by sample steel No. 24. Example 5 Three continuously cast slabs of 200 mm thickness and having a composition containing 3.0% of Si, 0.040% of C, 0.07% of Mn and 0.025% of S were heated at 1,320°C for 1 hour, hot rolled into a thickness of 3.0 mm, and then coiled. The hot rolled and coiled sheet were subjected to a normalizing annealing at 980°C for 30 seconds, cold rolled into a thickness of 0.80 mm, successively subjected to an intermediate annealing at 950°C for 2 minutes under an atmosphere of P H2 O/P H2 =0.003-0.35 by a commonly known method so as to remove 0.003%, 0.012% or 0.024% (decarburized amount ΔC) of carbon, and then finally cold rolled into a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing, and then to a final annealing at 1,200°C for 10 hours. The finally annealed sheets were provided with an insulating coating to obtain grain-oriented silicon steel sheets. The magnetic properties of the products are shown in the following Table 7. It can be seen from Table 7 that, in sample steel No. 26, whose decarburized amount ΔC is less than the lower limit of the range of 0.006-0.020% defined in the present invention, the texture of the resulting steel sheet contains 15% of fine grains, a low iron loss value can not be obtained, and moreover the magnetic induction is low; while, in sample steel No. 28, whose decarburized amount ΔC is 0.024% (which is more than the upper limit of the above described range), although the texture of the resulting steel sheet does not contain fine grains, a sufficiently low iron loss value can not be obtained. On the contrary, in sample steel No. 27, whose decarburized amount is within the range defined in the present invention and which satisfies the other requirements, the resulting steel sheet has a satisfactorily low iron loss value and a very high magnetic induction. Example 6 Three slabs of 200 mm thickness and having a composition containing 3.3% of Si, 0.048% of C, 0.05% of Mn, 0.03% of Se and 0.03% of Sb were produced by a continuous casting of a molten steel, heated at 1,380°C for 1 hour, hot rolled into a thickness of 2.5 mm, and then coiled. Immediately, the coiled sheets were subjected to a hot rolled sheet-annealing at 750°C for 5 hours in boxes, the atmospheres in the boxes being kept to three different levels. In sample steel No. 29, the coiled sheet was treated in a dry N₂ atmosphere, and 0.003% of C was removed. In sample steel No. 30, the coiled sheet was annealed in air having a dew point of 20°C, and 0.013% of C was removed. In sample steel No. 31, the coiled sheet was annealed in air having a dew point of 40°C, and 0.026% of C was removed. Then, the above treated coiled sheets were subjected to a normalizing annealing at 980°C for 30 seconds, cold rolled into a thickness of 0.75 mm, successively subjected to an intermediate annealing at 950°C for 2 minutes, and then finally cold rolled at a reduction rate of 60% to obtain finally cold rolled sheets having a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing at 800°C in wet hydrogen, treated with an annealing separator consisting mainly of MgO, subjected to a final annealing at 1,200°C for 10 hours, and then provided with an insulating coating to produce grain-oriented silicon steel sheets. The magnetic properties of the products are shown in the following Table 8. It can be seen from Table 8 that, in sample steel No. 29, whose decarburized amount ΔC is 0.003%, (which is less than the lower limit of the range defined in the present invention), the texture of the resulting steel sheet contains as much as 30% of fine grains, and satisfactory magnetic properties can not be obtained; while, in sample steel No. 31, whose decarburized amount ΔC is 0.026%, (which is more than the upper limit of the defined range), the texture of the resulting steel sheet contains no fine grains but contains coarse secondary recrystallized grains. Although the steel sheet has a satisfactorily high magnetic induction it does not have a satisfactorily low iron loss value. On the contrary, in sample steel No. 30, which satisfies all the requirements defined in the present invention, the resulting steel sheet has concurrently a low iron loss value and a high magnetic induction. Therefore, according to the present invention, a satisfactory grain-oriented silicon steel sheet can be obtained. Example 7 Three slabs of 200 mm thickness having a composition containing 3.35% of Si, 0.050% of C, 0.05% of Mn, 0.03% of Se and 0.03% of Sb were produced by a continuous casting of a molten steel, heated at 1,380°C for 1 hour, hot rolled into a thickness of 2.5 mm, and then coiled. The coiled sheets were pickled in a 10% H₂SO₄ bath kept at 80°C, subjected to a normalizing annealing at 980°C for 30 seconds under a continuous annealing atmosphere of P H2O /P H2 =0.003-0.35 by a commonly known method so as to remove 0.002%, 0.013% or 0.027% (decarburized amount ΔC) of carbon, cold rolled into a thickness 0.75 mm, subjected to an intermediate annealing at 950°C for 2 minutes, and then finally cold rolled at a reduction rate of 60% to obtain finally cold rolled sheets having a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing at 800°C in wet hydrogen, treated with an annealing separator consisting mainly of MgO, subjected to a final annealing at 1,200°C for 10 hours, and then provided with an insulating coating to produce grain-oriented silicon steel sheets. The magnetic properties of the products are shown in the following Table 9. It can be seen from Table 9 that, in sample steel No. 32, whose decarburized amount ΔC is 0.002%, (which is less than the lower limit of the range defined in the present invention), the texture of the resulting steel sheet contains as much as 30% of fine grains, and a steel sheet having a satisfactory low iron loss value and a high magnetic induction B₁₀ can not be obtained; while, in sample steel No. 34, whose decarburized amount ΔC is 0.027% (which is more than the upper limit of the defined range), the texture of the resulting steel sheet contains no fine grains but contains coarse secondary recrystallized grains. Although the steel sheet has a satisfactorily high magnetic induction it does not have a satisfactorily low iron loss. On the contrary, in sample steel No. 33, which satisfies all the requirements defined in the present invention, the resulting steel sheet has concurrently a low iron loss value and a high magnetic induction. Therefore, according to the present invention, a satisfactory grain-oriented silicon steel sheet can be obtained. Example 8 Three slabs of 200 mm thickness having a composition containing 3.3% of Si, 0.048% of C, 0.05% of Mn, 0.03% of Se and 0.03% of Sb were produced by continuous casting of molten steel, heated at 1,380°C for 1 hour, hot rolled into a thickness of 2.5 mm, and then coiled. In sample steel No. 35, both a normalizing annealing at 980°C for 30 seconds and an intermediate annealing at 950°C for 2 minutes before the final cold rolling were carried out under a non-oxidizing atmosphere of P H2 O/P H2 =0.003 to remove 0.003% in total (total decarburized amount ΔC) of carbon. In sample steel No. 36, after the coiled sheet was pickled in a 10% H₂SO₄ bath kept at 80°C, both the normalizing annealing at 980°C for 30 seconds and the intermediate annealing at 950°C for 2 minutes were carried out under an atmosphere of P H2 O/P H2 =0.05 to remove 0.005% of C during the normalizing annealing and 0.008% of C during the intermediate annealing (total decarburized amount ΔC was 0.013%). In sample steel No. 37, after the coiled sheet was pickled in a 10% H₂SO₄ bath kept at 80°C, both the normalizing annealing at 980°C for 30 seconds and the intermediate annealing at 950°C for 2 minutes were carried out under an atmosphere of P H2 O/P H2 =0.15 to remove 0.012% of C during the normalizing annealing and 0.016% of C during the intermediate annealing (total decarburized amount ΔC was 0.028%). After the above described normalizing annealing, the coiled sheets were cold rolled into a thickness of 0.75 mm, subjected to the above described intermediate annealing, and then finally cold rolled at a reduction rate of 60% to obtain finally cold rolled sheets having a final gauge of 0.30 mm. The finally cold rolled sheets were subjected to a decarburization annealing at 800°C in wet hydrogen, treated with an annealing separator consisting mainly of MgO, subjected to a final annealing at 1,200°C for 10 hours, and then applied with an insulating coating to produce grain-oriented silicon steel sheets. The magnetic properties of the products are shown in the following Table 10. It can be seen from Table 10 that the resulting steel sheet of sample steel No. 36 of the present invention has satisfactorily low iron loss value and high magnetic induction. In sample steel No. 35 whose decarburized amount is short, and in sample steel No. 37 whose decarburized amount is excess, the desired magnetic properties can not be obtained. It can be seen from the above described examples that, when all the requirements defined in the present invention are satisfied, a grain-oriented silicon steel sheet having excellent magnetic properties, that is, having satisfactorily low iron loss value and high magnetic induction can be stably produced. Thus the present invention is very useful in the production of transformer and other electric instruments having a low iron loss and a high efficiency. There have hitherto been proposed various methods in the production of grain-oriented silicon steel sheets. However, in the conventional methods, during the high temperature heating of the slab, particularly continuously cast slab, the crystal grains are apt to be coarse, and the formation of so-called fine grain streaks can not be stably prevented. Thus grain-oriented silicon steel sheets having excellent magnetic properties can not be stably produced on a commercial scale. On the contrary, according to the present invention, the composition of the slab to be used as the starting material is limited, and particularly the C content is properly adjusted depending upon the Si content, and at the same time the final cold rolling is carried out at a reduction rate of 40-80% to form a uniform crystal texture and to promote the predominant development of secondary recrystallized grains of (110)[001] orientation in the recrystallization texture. Further 0.006-0.020% of C is removed from the steel after completion of the hot rolling and before the beginning of the final cold rolling, whereby silicon steel sheets having excellent magnetic properties can be stably produced.

Claims: A method of producing a grain-oriented silicon steel sheet having excellent magnetic properties from a continuously cast slab, comprising the steps of (i) forming a hot rolled steel sheet by hot rolling a continuously cast slab of silicon steel consisting of from 2.8 to 4.0% by weight of Si, 0.02 to 0.15% by weight of Mn, 0,0060.080% by weight in total of at least one of S and Se, and C within the range defined by the following formula 0.37[Si%]+0.27≦log([C%]×10³)≦0.37[Si%]+0.57 wherein [Si%] and [C%] represent the contents (% by weight) of Si and C in the silicon steel, respectively, with the balance being Fe, incidental impurities and optionally grain boundary elements; (ii) coiling the hot rolled steel sheet; (iii) subjecting the coiled steel sheet to two or more cold rollings with an intermediate annealing between them and using a reduction rate of from 40 to 80% in the final cold rolling to produce a finally cold rolled steel sheet having a final gauge; and (iv) subjecting the finally cold rolled steel sheet to decarburization annealing and final annealing; the method including the step of removing 0.006-0.020% by weight of C from the steel after the completion of the above described hot rolling step and before the beginning of the above described final cold rolling. A method according to claim 1, wherein said 0.006-0.020% by weight of C is removed from the steel by means of a decarburization treatment carried out after the coiling step and before the cold rolling. A method according to claim 1, wherein said 0.006-0.020% by weight of C is removed from the steel during the intermediate annealing step carried out before the final cold rolling. A method according to claim 1, wherein said 0.006-0.020% by weight of C in total is removed from the steel by means of a decarburization treatment, which is carried out after the coiling step and before the cold rolling, and during the intermediate annealing step carried out before the final cold rolling. A method according to claim 1 and including the additional step of subjecting the coiled steel to a normalizing annealing before the cold rolling wherein said 0.006-0.020% by weight of C is removed from the steel during the normalizing annealing. A method according to claim 1 and including the additional steps of subjecting the coiled steel sheet to box annealing and then to normalizing annealing before the cold rolling wherein said 0.006-0.020% by weight of C is removed from the steel during the normalizing annealing. A method according to claim 4 and including the additional step of subjecting the coiled steel to a normalizing annealing before the cold rolling wherein said 0.006-0.020% by weight of C in total is removed from the steel in at least one of the decarburization treatment after coiling, the normalizing annealing, and the intermediate annealing before the final cold rolling. A method according to claim 7 and including the additional step of subjecting the coiled sheet to a box annealing before the cold rolling wherein said 0.006-0.020% by weight of C in total is removed from the steel in at least one of the decarburization treatment after the coiling, the box annealing, the normalizing annealing, and the intermediate annealing before the final cold rolling.

Inventors: GOTO TOMOMICHI, IIDA YOSHIAKI, IWAMOTO KATSUO, KOBAYASHI YOHINORI, MATOBA ISAO, GOTO, TOMOMICHI, IIDA, YOSHIAKI, IWAMOTO, KATSUO, KOBAYASHI, YOHINORI, MATOBA, ISAO
Applicants: KAWASAKI STEEL CO, KAWASAKI STEEL CORPORATION
Application year: 1982
Main classification: H01F1
IPC codes: C22C38, H01F1, C21D8