JP2006213993A - Method for producing grain oriented electromagnetic steel plate - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a grain oriented electromagnetic steel plate having excellent magnetic properties free from variation, in the case secondary recrystallization is caused, so as to be the grain oriented electromagnetic steel sheet without the incorporation of inhibitors, by allowing the secondary recrystallization to stably appear. <P>SOLUTION: At the time when a grain oriented electromagnetic steel sheet is produced using a slab having a composition comprising, by mass, 0.020 to 0.080% C, 2.0 to 8.0% Si, and 0.005 to 3.0% Mn, and in which the content of sol.Al is reduced to <0.0120%, S and Se to <0.0040%, respectively, and N to <0.0060%, and the balance Fe with inevitable impurities as the stock, the heating of the slab is performed to 1,100°C in such a manner that the temperature rising rate at which the surface temperature of the slab lies in the range of 850 to 1,100°C is controlled to 100 to 450°C/h, and is next subjected to soaking treatment at 1,100 to 1,250°C for 10 to 120 min, and, directly after the soaking, the slab composed of two phases of an α phase and a γ phase is extracted from the furnace, and hot rolling is started. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to a method for producing a grain-oriented electrical steel sheet used mainly for a core material of a power transformer at low cost.

  Oriented electrical steel sheets are mainly used as iron cores for transformers and other electrical equipment, and it is basically important to have excellent magnetic properties such as magnetic flux density and iron loss value in order to adapt to such applications. Therefore, what is important in the production of grain-oriented electrical steel sheets is to highly accumulate the orientation of crystal grains secondary recrystallized by so-called finish annealing in the {110} <001> orientation, so-called Goth orientation. .

  As a general technique for effectively promoting the accumulation of such secondary recrystallization, there is a method using a precipitate called an inhibitor. For example, a method using AlN and MnS described in Patent Document 1 and a method using MnS and MnSe described in Patent Document 2 are typical examples, and these are industrially put into practical use. Apart from these, a number of techniques are known such as a technique for adding CuSe and BN is described in Patent Document 3 and a method using a nitride of Ti, Zr, and V is described in Patent Document 4.

  The method using these inhibitors is a useful method for stably developing secondary recrystallized grains, but the slab heating temperature before hot rolling is 1300 ° C. or higher because it is necessary to finely disperse precipitates. Must be done at high temperatures. However, high-temperature heating of the slab not only increases the equipment cost, but also increases the amount of scale generated during hot rolling, which not only reduces yield but also increases problems such as equipment maintenance. It was difficult to meet the demand for manufacturing cost reduction.

On the other hand, as a method for producing a grain-oriented electrical steel sheet without using an inhibitor, for example, techniques described in Patent Document 5, Patent Document 6, Patent Document 7, and Patent Document 8 are known. What is common to these techniques is that the {110} plane is intended to grow preferentially using surface energy as the driving force. In order to effectively use the surface energy difference, it is necessary to reduce the plate thickness in order to increase the contribution of the surface. For example, in the technique disclosed in Patent Document 5, the plate thickness is limited to 0.2 mm or less, and in the technique disclosed in Patent Document 6, the plate thickness is limited to 0.15 mm or less.
Since the thickness of the grain-oriented electrical steel sheets currently used is almost 0.20 mm or more, it is difficult to obtain a normal product by the method using the surface energy as described above.

Furthermore, in order to utilize the surface energy, it is necessary to perform high-temperature final finish annealing in a state in which the generation of surface oxides is suppressed. For example, in the technique disclosed in Patent Document 5, it is necessary to perform the annealing at a temperature of 1180 ° C. or higher in a vacuum or in an inert gas, hydrogen gas, or a mixed gas of hydrogen gas and nitrogen gas. Yes. In the technique disclosed in Patent Document 6, it is recommended to further reduce the pressure in an inert gas atmosphere or hydrogen gas or a mixed atmosphere of hydrogen gas and inert gas at a temperature of 950 to 1100 ° C. Furthermore, in the technique disclosed in Patent Document 8, it is necessary to perform final finish annealing in a non-oxidizing atmosphere or vacuum with an oxygen partial pressure of 0.5 Pa or less at a temperature of 1000 to 1300 ° C.
As described above, in order to obtain good magnetic properties using surface energy, an inert gas or hydrogen is used as the atmosphere of final finish annealing, and a vacuum is further required as a recommended condition. However, compatibility between high temperature and vacuum is difficult in terms of equipment and increases costs.

  Furthermore, when surface energy is used, in principle, only the {110} plane can be selected, and the growth of only goth grains with the <001> direction aligned in the rolling direction is not selected. . Since the magnetic properties of a grain-oriented electrical steel sheet improve only when the easy magnetization axis <001> is aligned in the rolling direction, good magnetic properties cannot be obtained in principle only by selecting the {110} plane. Therefore, rolling conditions and annealing conditions that can obtain good magnetic properties by a method using surface energy are limited, and as a result, the magnetic properties become unstable.

In order to solve the above problem, the applicant proposed in Patent Document 9 a method for producing a grain-oriented electrical steel sheet having excellent magnetic properties at low cost by slab heating at a lower temperature than in the past.
In other words, as a result of earnest research on the technology for generating secondary recrystallization without containing an inhibitor in the slab and increasing the sharpness of the secondary recrystallized grains in the Goth orientation, the content of impurities was mainly reduced. By suppressing, it came to discover that a secondary recrystallization could be expressed stably, even if an inhibitor is not contained in a slab.
According to this technique, since an inhibitor component is not required, high-temperature slab heating intended for solid solution of the inhibitor component is not necessary, and a reduction in the slab heating temperature is realized.

  However, when the technique disclosed in Patent Document 9 is carried out on an industrial scale, it has been found that the magnetic properties of the obtained steel sheet vary and stable production is difficult.

  In addition, in high-temperature heating of slabs containing inhibitors, as described in Patent Document 10, Patent Document 11, Patent Document 12, etc., the rate of temperature increase during slab heating has been studied, but it contains inhibitor. Regarding the low temperature heating of the slabs that do not, the temperature rise rate has not been studied.

Japanese Patent Publication No. 40-15644 Japanese Patent Publication No.51-13469 Japanese Patent Publication No.58-42244 Japanese Patent Publication No.46-40855 JP-A-64-55339 JP-A-2-57635 Japanese Unexamined Patent Publication No. 7-76732 Japanese Unexamined Patent Publication No. 7-197126 Open 2000-129356 Japanese Unexamined Patent Publication No. 7-316657 JP-A-8-176665 JP-A-8-333631

As described above, when the technique disclosed in Patent Document 9 is implemented on an industrial scale, the magnetic properties of the obtained steel sheet vary and stable production is difficult.
The present invention advantageously solves the above-mentioned problems, and stably produces secondary recrystallization when a secondary recrystallization is generated without containing an inhibitor to obtain a grain-oriented electrical steel sheet. An object of the present invention is to propose a method capable of advantageously producing a grain-oriented electrical steel sheet having excellent magnetic characteristics without variation.

The elucidation process of the present invention will be described below.
A major difference between conventional high-temperature heating of about 1300 ° C or higher and slab low-temperature heating of 1250 ° C or lower in the present invention is that the phase after heating becomes α single phase in conventional slab high-temperature heating, whereas the present invention In the slab low-temperature heating in, a two-phase coexistence state of α phase and γ phase can be mentioned.
And in this invention, since it does not contain an inhibitor, in order to prevent the coarsening of the crystal grain of a hot-rolled sheet, it is thought that the function of (gamma) phase becomes very important.

  Usually, in the slab high-temperature heating that becomes an α single phase, the elements present in the slab are uniformly dispersed if heating is performed for a time sufficient to achieve a thermodynamic equilibrium state. The time sufficient to reach the thermodynamic equilibrium state is considered to be a time during which the elements present in the slab can sufficiently diffuse, so it is considered to be relatively short at a high temperature.

On the other hand, in the slab low temperature heating, heating is performed in a two-phase region of an α phase and a γ phase. In this two-phase coexistence state, even if an equilibrium state is reached, the concentration of elements present in the slab differs between the α phase and the γ phase. For example, in the case of Fe-1.8 mass% Si (C: 0 mass%), according to the equilibrium diagram, it becomes α single phase (Si: 1.8 mass%) at a high temperature of 1400 ° C, but lower than this. At 1150 ° C, there are two phases, an α phase with a Si concentration of 1.95 mass% and a γ phase with a Si concentration of 1.65 mass%. Therefore, by heating for a long time, the elements present in the slab are distributed to the respective concentrations in the equilibrium state in the α phase and the γ phase as described above. Therefore, in the case of slab low-temperature heating, there arises a new problem that the degree of concentration distribution is uneven depending on the position in the slab.
Therefore, the inventors investigated the extent of this non-uniformity in the following experiment.

A 40 mm square sample was cut out from a slab having a thickness of 250 mm containing C: 0.04 mass%, Si: 3.4 mass%, and Mn: 0.07 mass%, and the sample was soaked at 1200 ° C. for 60 minutes and then cooled with water. The cross section of the sample was mirror-finished by polishing, then corroded with 3% NHO ₃ nital solution, and observed with an optical microscope.
As a result, a plurality of regions each having a diameter of about 2 mm composed of a group of a plurality of small black portions of about 50 μm were observed. Here, a small black portion of about 50 μm is a carbide, and a region including a diameter of about 2 mm including these carbides is considered to be a region that was a γ phase at the time of soaking. That is, at the end of soaking, it is considered that the γ phase having a diameter of about 2 mm was present in the α phase, and the non-uniformity due to the γ phase is thought to exist with a length of about 2 mm.

By the way, when the diffusion coefficient of C and Si in α-Fe: D, which is a standard of the diffusion distance (D × time) ^0.5 is calculated in the case of temperature: 1200 ° C. and time: 60 minutes, C is about 3 mm. , Si becomes about 70μm.
The diffusion coefficient D was calculated using the previous exponent term and activation energy in the revised 4th edition metal data book (Maruzen Co., Ltd., 2004).

Therefore, when performing soaking at 1200 ° C for 60 minutes, which corresponds to low-temperature slab heating, the diffusion rate of the α-phase and the γ-phase with a diameter of about 2 mm arising from the α-phase is considered if the diffusion rate is taken into consideration. Large C has sufficient concentration distribution, but Si with low diffusion rate is difficult to perform concentration distribution, and the degree of concentration distribution may be uneven in the slab due to the size of the γ phase. It is considered that the nature is high.
In other words, the inventors, in particular, that Si, which is the main component, is in a non-equilibrium state in which concentration distribution is incomplete as described above, and the degree thereof is uneven in the slab. I guessed.

  Based on this estimation, it is considered effective to bring the slab soaking closer to the equilibrium state in order to stabilize the magnetic characteristics. As a method of bringing the slab closer to the equilibrium state, it is conceivable that the slab is soaked for a long time. However, soaking for a long time makes the slab crystal grain size coarse, making it difficult to recrystallize during hot rolling, and recrystallized grains tend to be coarse even after recrystallization, making them inappropriate for secondary recrystallization. Since the {100} <110> orientation, a so-called oblique cube orientation, is developed, the magnetic properties may be deteriorated.

Therefore, the inventors conceived that the rate of temperature rise was slowed in the process of soaking at the time of slab heating, and conducted an experiment for changing the rate of temperature rise during heating. The rate of temperature increase was changed in the range from 850 ° C. at which the γ phase began to form to 1100 ° C. at which the amount of γ phase almost reached the maximum (see Trans. ASM (1961) 53, 715, etc.).
The details of the experiment are described below.

  50 slabs having a thickness of 220 mm and a width of 1100 mm containing C: 0.04 mass%, Si: 3.3 mass% and Mn: 0.07 mass% were produced by continuous casting. Each of these 10 slabs was heated in a gas combustion furnace at an average speed from 850 ° C to 1100 ° C at 250 ° C / h, 350 ° C / h, 450 ° C / h, 550 ° C / h, and 650 ° C / h. Soaked at 1100 ° C or higher for 60 minutes. After that, half of the 10 slabs were subjected to width reduction with a reduction ratio of 9%, and half were subjected to rough rolling without width reduction to a sheet bar with a thickness of 40 mm, followed by finish rolling. After being made into a hot-rolled sheet with a thickness of 2.2 mm, it was wound around a coil.

Furthermore, all these hot-rolled sheets were annealed at 1000 ° C. for 30 seconds, quenched at a rate of 35 ° C./s, pickled, and finished to a thickness of 0.28 mm by cold rolling at 240 ° C. Then, after degreasing, decarburization annealing was performed at 840 ° C. for 2 minutes.
After that, an annealing separator containing 5 mass% of TiO ₂ in MgO was applied to both sides of the steel sheet with a coating amount of 8 g / m ^{2 on} one side, and the final finish annealing was held at 850 ° C. for 48 hours in N ₂ gas. After that, the temperature was raised to 900 ° C at a rate of 5 ° C / h, the atmosphere gas was changed from N ₂ gas to H ₂ gas, the temperature was raised to 1150 ° C at a rate of 25 ° C / h, and 1190 ° C for 8 hours. After holding, the temperature was lowered to 600 ° C. in H ₂ gas, and from 600 ° C., the temperature was lowered in Ar gas.
Then, after removing the unreacted annealing separator, a magnesium phosphate solution containing 50 mass% colloidal silica in a solid content ratio was applied as a tension coating solution, and then baked at 840 ° C. for 30 seconds to obtain a product plate.

The results of examining the magnetic properties of the product plate thus obtained are shown in FIG.
As is clear from the figure, when the average speed between 850 ° C. and 1100 ° C. is 450 ° C./h or less, the magnetic characteristics are good and the variation is small. In particular, it was found that when the width reduction was performed prior to hot rolling, the magnetic properties were even better and the variation was small.

  Even if the heating rate is 450 ° C / h, the magnetic properties have improved as described above, even though the time is not sufficient for Si to diffuse by about 2 mm. This is probably because the uniformity is large, and by controlling the rate of temperature increase, there is no adverse effect such as soaking for a long time, and a sufficient improvement in magnetic properties is achieved.

The reason why the magnetic characteristics are further improved by the width reduction is not necessarily clear, but can be estimated as follows.
Since the present invention does not contain an inhibitor, it cannot be considered that the precipitation state of the inhibitor was affected by the reduction. Therefore, it is considered that the state of the crystal grains or the γ phase changed due to the width reduction. In addition, it is considered that the state of the γ phase has changed since the magnetic properties were improved particularly when the temperature rise rate was slowed down and width reduction was performed.
In other words, the width reduction and the subsequent horizontal reduction increase the diffusion of solid solution elements in the slab, and promotes the sufficient distribution of elements such as Si in the α and γ phases, resulting in increased stability. It is considered a thing. Here, it is estimated that this effect does not appear sufficiently when the slab is pressed down only horizontally and the deformation direction is the same.

As described above, in order to stably improve the magnetic properties, it is important to slowly heat the temperature range where the γ phase is generated, and further, it is effective to apply a width reduction of 5% or more after slab soaking. Is.
The present invention has been completed based on the above findings.

That is, the present invention
(1) C: 0.020 to 0.080 mass%, Si: 2.0 to 8.0 mass%, Mn: 0.005 to 3.0 mass%, sol.Al less than 0.0120 mass%, S and Se less than 0.0040 mass%, N After reducing the slab to less than 0.0060 mass%, the balance being Fe and inevitable impurities composition, hot rolling after slab heating, and then performing one or more cold rollings sandwiching intermediate annealing In producing a grain-oriented electrical steel sheet by performing decarburization annealing and then applying final annealing by applying an annealing separator,
In the above slab heating, the surface temperature of the slab is heated to 1100 ° C at a heating rate of 850 to 1100 ° C at 100 to 450 ° C / h, and then subjected to a soaking treatment at 1100 to 1250 ° C for 10 to 120 minutes. A method for producing a grain-oriented electrical steel sheet, characterized in that a slab consisting of two phases of an α phase and a γ phase is extracted from a furnace immediately after soaking and hot rolling is started.

(2) After the slab is extracted from the furnace, the horizontal reduction in the hot rolling is started after the width reduction of the reduction ratio: 5% or more is performed in the temperature range where the surface temperature of the slab is 1000 ° C. or more. The method for producing a grain-oriented electrical steel sheet according to (1) above.

(3) The slab further comprises Ni: 0.01-1.50 mass%, Cu: 0.01-0.50 mass%, Sn: 0.005-0.50 mass%, Sb: 0.005-0.50 mass%, P: 0.005-0.50 mass%, and Cr. : A method for producing a grain-oriented electrical steel sheet according to (1) or (2), wherein the composition contains at least one selected from 0.01 to 1.50 mass%.

  ADVANTAGE OF THE INVENTION According to this invention, it becomes possible to manufacture the grain-oriented electrical steel plate excellent in the magnetic characteristic industrially stably and cheaply, and the industrial value is very high.

The present invention will be specifically described below.
First, the reason why the slab component composition is limited to the above range in the present invention will be described.
C: 0.020-0.080 mass%
If the amount of C exceeds 0.080 mass%, it becomes difficult to reduce to less than 0.0050 mass% at which no magnetic aging occurs during decarburization annealing, so the amount of C is limited to 0.080 mass% or less. On the other hand, C is required to be 0.020 mass% or more in order to obtain a two-phase coexistence state of α phase and γ phase after slab heating.

Si: 2.0-8.0mass%
Si is an effective component for increasing the specific resistance of steel sheets and reducing iron loss. However, when the content exceeds 8.0 mass%, the cold-rolling property is impaired, whereas when the content is less than 2.0 mass%, the specific resistance decreases. In addition, the crystal orientation is randomized by the α → γ transformation during the final finish annealing, and a sufficient iron loss reduction effect cannot be obtained. For this reason, Si amount is taken as 2.0 to 8.0 mass%.

Mn: 0.005-3.0mass%
Mn is an element necessary for improving the hot workability. However, if the content is less than 0.005 mass%, the effect of addition is poor, while if it exceeds 3.0 mass%, the magnetic flux density decreases. Is in the range of 0.005 to 3.0 mass%.

sol.Al: less than 0.0120 mass%
If Al is present in excess, secondary recrystallization becomes difficult. In particular, when sol.Al is 0.0120 mass% or more, secondary recrystallization hardly occurs and magnetic properties are deteriorated, so sol.Al needs to be suppressed to less than 0.0120 mass%.

S and Se: each less than 0.0040 mass% When S and Se are respectively present at 0.0040 mass% or more, secondary recrystallization becomes difficult. This is because MnS and MnSe coarsened by slab heating make the primary recrystallized structure non-uniform. Accordingly, the S and Se contents must be suppressed to less than 0.0040 mass%, respectively.

N: Less than 0.0060 mass% When N is present in an excessive amount, as in S and Se, secondary recrystallization becomes difficult. In particular, when N is 0.0060 mass% or more, secondary recrystallization hardly occurs and the magnetic properties deteriorate, so it is necessary to suppress it to less than 0.0060 mass%.

  Others are Fe and inevitable impurities. Among the inevitable impurities, Ti, Nb, B, Ta, V and the like, which are nitride forming elements, are each effective for stabilizing secondary recrystallization to be reduced to less than 0.0050 mass%.

  As described above, the essential component and the suppression component have been described. In addition, in the present invention, one or more selected from Ni, Cu, Sn, and Sb are selected from the viewpoint of improving the magnetic properties more stably industrially. In addition, from the viewpoint of stabilizing the formation of the forsterite film, one or two selected from P and Cr can be appropriately contained in the content ranges shown below.

Ni: 0.01-1.50 mass%
Ni is an element useful for improving the magnetic properties by improving the hot-rolled sheet structure. However, if the content is less than 0.01 mass%, the improvement in magnetic properties is small. On the other hand, if it exceeds 1.50 mass%, secondary recrystallization becomes unstable and the magnetic properties deteriorate, so Ni is in the range of 0.01 to 1.50 mass%. It is preferable to contain.

Cu: 0.01-0.50mass%
Cu is a useful element that suppresses nitriding and oxidation of the steel sheet during final finish annealing, promotes secondary recrystallization of crystal grains having a good crystal orientation, and improves magnetic properties. For that purpose, it is desirable to contain 0.01 mass% or more. On the other hand, when Cu is contained in excess of 0.50 mass%, hot rollability deteriorates, so it is desirable to contain Cu with an upper limit of 0.50 mass%.

Sn: 0.005-0.50mass%
Sn is a useful element that suppresses nitriding and oxidation of the steel sheet during final finish annealing, promotes secondary recrystallization of crystal grains having a good crystal orientation, and improves magnetic properties. For that purpose, it is desirable to contain 0.005 mass% or more. On the other hand, when Sn is contained in excess of 0.50 mass%, the cold rolling property is deteriorated. Therefore, Sn is desirably contained with an upper limit of 0.50 mass%.

Sb: 0.005-0.50mass%
Sb is a useful element that suppresses nitriding and oxidation of the steel sheet during final finish annealing, promotes secondary recrystallization of crystal grains having a good crystal orientation, and improves magnetic properties. For that purpose, it is desirable to contain 0.005 mass% or more. On the other hand, if the Sb content exceeds 0.50 mass%, the cold rollability deteriorates. Therefore, it is desirable to contain Sb with an upper limit of 0.50 mass%.

P: 0.005-0.50mass%
P has a function of stabilizing the formation of the forsterite film. For that purpose, P is preferably contained in an amount of 0.005 mass% or more. On the other hand, when P exceeds 0.50 mass%, the cold rolling property deteriorates. Therefore, it is desirable that P is contained with an upper limit of 0.50 mass%.

Cr: 0.01 ~ 1.50mass%
Cr has a function of stabilizing the formation of the forsterite film. For that purpose, it is desirable to contain 0.01 mass% or more. On the other hand, if Cr is contained in excess of 1.50 mass%, secondary recrystallization becomes difficult and magnetic properties deteriorate, so Cr is desirably contained with an upper limit of 1.50 mass%.

Next, the manufacturing method of this invention is demonstrated.
The slab adjusted to the above suitable component composition range is produced by a normal ingot-making method and a continuous casting method. Further, a thin cast piece having a thickness of 100 mm or less may be manufactured by a direct casting method.

Next, the slab is heated and then subjected to hot rolling. In the present invention, this slab heating step is important.
That is, in the present invention, it is important that the rate of temperature increase from 850 ° C. to 1100 ° C. during slab heating is 100 ° C./h or more and 450 ° C./h or less. The reason for setting the heating rate to 450 ° C./h or less is to bring the slab closer to a thermodynamic equilibrium state, to make it stable, and to improve the magnetic properties of the product plate. The lower limit of the heating rate does not need to be specified in terms of characteristics, but if it is less than 100 ° C / h, the heating time becomes longer, which is disadvantageous for industrial production, so the lower limit was set to 100 ° C / h. . A more preferable temperature increase rate is in the range of 200 to 400 ° C./h.
Here, the rate of temperature rise refers to the average rate. That is, when the time when the surface temperature of the slab reaches 850 ° C. is T ₈₅₀ and the time when the surface temperature reaches 1100 ° C. is T ₁₁₀₀ , the rate of temperature increase is calculated by 250 ° C. ÷ (T ₁₁₀₀ −T ₈₅₀ ). .

  In addition, the reason why the temperature range of the heating rate is set to the range of 850 ° C to 1100 ° C is that, in this temperature range, the amount of γ phase in the thermodynamic equilibrium state increases as the temperature rises, so it approaches the thermodynamic equilibrium state. This is because sufficient time is required in this temperature range. The rate of temperature increase up to 850 ° C. may be determined in consideration of industrial productivity.

  Thereafter, after raising the temperature to 1100 ° C., soaking is performed for 10 minutes to 120 minutes in a temperature range of 1100 ° C. to 1250 ° C. Here, when the soaking temperature exceeds 1250 ° C, the crystal grain size of the slab becomes coarse, and it becomes difficult to recrystallize during hot rolling. Since the {100} <110> orientation which is an inappropriate orientation for the crystal, the so-called oblique cube orientation develops, the magnetic properties deteriorate. In addition, in the present invention, since no inhibitor is contained in the slab, fine precipitates are formed by re-dissolving and re-precipitating the precipitate-forming components that are inevitably mixed, which adversely affects the secondary recrystallization behavior. . Even if the soaking time exceeds 120 minutes, it is not preferable for the same reason. On the other hand, when the soaking temperature is less than 1100 ° C. and the soaking time is less than 10 minutes, the rolling load of hot rolling becomes high and hot rolling becomes difficult. Therefore, it is necessary to soak in the temperature range of 1100 ° C. or higher and 1250 ° C. or lower for 10 minutes to 120 minutes. A more preferable soaking time is 60 to 120 minutes. Note that soaking refers to the time when the surface temperature of the slab is 1100 ° C. or higher.

Here, the actual measured value of the surface temperature of the slab is preferable, but in reality, it is extremely difficult to actually measure the surface temperature of the slab in the furnace. It may be a value.
The slab heating may be performed using a gas combustion furnace, an electric heating furnace, or both.

For the slab that has been soaked, it is preferable to apply a width reduction of a reduction ratio of 5% or more under the condition that the surface temperature of the slab is 1000 ° C. or higher. Such width reduction is performed once or twice or more. When the width reduction is performed twice or more, the total value of the width reduction ratios may be 5% or more. Here, when the slab surface temperature during width reduction is less than 1000 ° C., the rolling load of hot rolling becomes high and hot rolling becomes difficult. Therefore, when the width reduction amount is less than 5%, sufficient magnetic properties are obtained. The improvement effect cannot be obtained.
Here, the preferred temperature at which the width reduction should be performed is 1100 ° C. or more, and the preferred reduction rate is 5 to 15%.

  Next, the slab is subjected to hot rough rolling and subsequently hot finish rolling to obtain hot rolled sheets. Hot rough rolling and hot finish rolling mainly consist of horizontal reduction, but width reduction for adjusting the plate width may be applied in the middle of the rolling.

  Next, hot-rolled sheet annealing is performed as necessary. In order to highly develop a goth structure in the product plate, it is preferable that the hot-rolled sheet annealing temperature is 800 ° C. or higher and 1200 ° C. or lower. If the hot-rolled sheet annealing temperature is less than 800 ° C., a band structure in hot rolling remains, and it becomes difficult to realize a primary recrystallized structure of sized particles, which inhibits the development of secondary recrystallization. On the other hand, if the annealing temperature of the hot-rolled sheet exceeds 1200 ° C, the precipitate forming components inevitably mixed in will dissolve and re-precipitate non-uniformly during cooling, making it difficult to achieve a sized primary recrystallized structure. Again, the development of secondary recrystallization is inhibited. Moreover, when the hot-rolled sheet annealing temperature exceeds 1200 ° C., it is extremely disadvantageous to realize the primary recrystallized structure of the sized particles because the grain size after the hot-rolled sheet annealing is too coarse.

  After hot-rolled sheet annealing, after cold rolling at least once with intermediate or intermediate annealing, decarburization annealing is performed, and C is 0.0080 mass% or less, preferably 0.0050 mass% or less, in which magnetic aging does not occur To reduce. Cold rolling may be performed at room temperature, but the temperature of the steel sheet is increased to 100 to 280 ° C, and aging treatment in the range of 100 to 280 ° C is performed once or a plurality of times during the cold rolling. This is effective in developing Gothic tissue.

  The decarburization annealing after the final cold rolling is preferably performed in a range of 700 to 1000 ° C. using a wet atmosphere. Moreover, you may use together the technique which increases Si amount by the siliconization method after decarburization annealing.

Thereafter, an annealing separator mainly composed of MgO is applied to perform final finish annealing, thereby developing a secondary recrystallized structure and forming a forsterite film. The final finish annealing needs to be performed at 800 ° C. or higher for secondary recrystallization. However, the heating rate up to 800 ° C. does not have a great influence on the magnetic properties, and may be under any conditions.
After final finish annealing, the shape is corrected by flattening annealing.
Furthermore, in order to improve iron loss, it is effective to provide an insulating coating that applies tension to the surface of the steel sheet.

Example 1
C: 0.05 mass%, Si: 3.5 mass%, Mn: 0.06 mass%, sol.Al: 0.0040 mass%, N: 0.0040 mass%, S: 0.0020 mass% and Se: 0.0002 mass%, the balance being Fe A slab having a thickness of 220 mm and a width of 1200 mm with an inevitable impurity composition was produced by a continuous casting method.
After these slabs were heated in a gas combustion furnace under the conditions shown in Table 1, some slabs were subjected to width reduction at 1120 ° C. Thereafter, rough rolling was performed to obtain a sheet bar having a thickness of 45 mm, and then finish rolling was performed to obtain a hot-rolled sheet having a thickness of 2.3 mm, which was wound around a coil.
Subsequently, all these hot-rolled sheets were annealed at 1000 ° C. for 30 seconds, quenched at a rate of 35 ° C./s, pickled, and then finished to a thickness of 0.28 mm by cold rolling.
Then, after degreasing, decarburization annealing was performed at 840 ° C. for 2 minutes in an atmosphere having a dew point of 60 ° C., a hydrogen concentration of 50 vol%, and a nitrogen concentration of 50 vol%.

After that, an annealing separator containing 8 mass% of TiO ₂ added to MgO was applied to both sides of the steel sheet at a coating amount of 5 g / m ^{2 on} one side, and then finally annealed at 860 ° C. for 48 hours in N ₂ gas. After holding, the temperature is raised to 900 ° C at a rate of 5 ° C / h, the atmospheric gas is changed from N ₂ gas to H ₂ gas, the temperature is raised to 1200 ° C at a rate of 25 ° C / h, and then 5 ° C at 1200 ° C. After maintaining the time, the temperature was lowered to 600 ° C. in H ₂ gas, and from 600 ° C., the temperature was lowered in Ar gas.
After removing the unreacted annealing separator after the above final finish annealing, a magnesium phosphate solution containing 50 mass% colloidal silica in a solid content ratio is applied as a tension coating solution, and baked at 840 ° C. for 30 seconds. A product plate was used. In addition, the product plate produced two coils of about 10 tons under each condition.

In each product plate thus obtained, the magnetic properties at both ends and the center in the longitudinal direction of the coil were evaluated by the magnetic flux density B ₈ when excited at 800 A / m.
Table 1 shows the maximum value, the minimum value, and the average value of the magnetic flux density B ₈ measured at six points under each condition.

  As shown in Table 1, all of the product plates produced according to the present invention had little variation in magnetic properties and excellent average property values.

Example 2
A slab having a thickness of 210 mm and a width of 1300 mm containing the components shown in Table 2 with the balance of Fe and inevitable impurities was produced by a continuous casting method.
These slabs were heated in a gas combustion furnace at an average rate of 500 ° C / h from 500 ° C to 850 ° C, and from 850 ° C to 1100 ° C at an average rate of 200 ° C / h. A soaking treatment was performed in the range of 1100 ° C to 1250 ° C for 60 minutes. The temperature averaged over time in this soaking was 1200 ° C.
Next, after carrying out width reduction at 1150 ° C., a sheet bar having a thickness of 40 mm was obtained by rough rolling, and subsequently a hot rolled sheet having a thickness of 2.1 mm was obtained by finish rolling, and then wound on a coil.
Thereafter, all these hot-rolled sheets were annealed at 1030 ° C. for 30 seconds, then rapidly cooled at a rate of 40 ° C./s, pickled, and finished to a thickness of 0.30 mm by cold rolling.

Then, after degreasing, decarburization annealing was performed at 850 ° C. for 1 minute in an atmosphere having a dew point of 55 ° C., a hydrogen concentration of 50 vol%, and a nitrogen concentration of 50 vol%.
After that, an annealing separator containing 3 mass% of TiO ₂ in MgO was applied to both sides of the steel sheet at a coating amount of 7 g / m ^{2 on} one side, and then final annealing was performed at 870 ° C. in N ₂ gas for 40 hours. After holding, the temperature is raised to 900 ° C at a rate of 5 ° C / h, the atmosphere gas is changed from N ₂ gas to H ₂ gas, the temperature is raised to 1180 ° C at a rate of 20 ° C / h, and then 8 ° C at 1180 ° C. After maintaining the time, the temperature was lowered to 600 ° C. in H ₂ gas, and from 600 ° C., the temperature was lowered in Ar gas.
After the above final finish annealing, after removing the unreacted annealing separator, a magnesium phosphate solution containing 50 mass% colloidal silica in a solid content ratio is applied as a tension coating solution, and baked at 840 ° C. for 30 seconds. A product plate was used. In addition, the product plate produced two coils of about 10 tons under each condition.

In each product plate thus obtained, the magnetic properties at both ends and the center in the longitudinal direction of the coil were evaluated by the magnetic flux density B ₈ when excited at 800 A / m.
Table 2 shows the maximum value, minimum value, and average value of the magnetic flux density B ₈ measured at six points under each condition.

  As is apparent from Table 2, all the product plates produced according to the present invention had little variation in magnetic properties and excellent average property values.

It is a figure which shows the relationship between the average temperature increase rate of the slab surface between 800-1100 degreeC at the time of slab heating, and the magnetic characteristic of a product board.

Claims (3)

C: 0.020 to 0.080 mass%, Si: 2.0 to 8.0 mass%, Mn: 0.005 to 3.0 mass%, sol.Al is less than 0.0120 mass%, S and Se are each less than 0.0040 mass%, N is 0.0060 mass% The slab with a composition of Fe and inevitable impurities in the balance is reduced to less than that, hot-rolled after slab heating, and then cold-rolled once or twice with intermediate annealing, and then decarburized. In producing a grain-oriented electrical steel sheet by annealing and then applying a final finish annealing by applying an annealing separator,
In the above slab heating, the surface temperature of the slab is heated to 1100 ° C at a heating rate of 850 to 1100 ° C at 100 to 450 ° C / h, and then subjected to a soaking treatment at 1100 to 1250 ° C for 10 to 120 minutes. A method for producing a grain-oriented electrical steel sheet, characterized in that a slab consisting of two phases of an α phase and a γ phase is extracted from a furnace immediately after soaking and hot rolling is started.   After the slab is extracted from the furnace, the horizontal reduction in the hot rolling is started after the rolling reduction: 5% or more in the temperature range where the surface temperature of the slab is 1000 ° C or more. Item 2. A method for producing a grain-oriented electrical steel sheet according to Item 1.   The slab further comprises Ni: 0.01-1.50 mass%, Cu: 0.01-0.50 mass%, Sn: 0.005-0.50 mass%, Sb: 0.005-0.50 mass%, P: 0.005-0.50 mass%, and Cr: 0.01- The method for producing a grain-oriented electrical steel sheet according to claim 1 or 2, wherein the composition contains at least one selected from 1.50 mass%.

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