CZ368496A3 - Process for steel sheet with oriented crystals, particularly for transformers - Google Patents

Abstract

Electrical steel sheet is made by concasting steel of composition in wt. %:- 0.02-0.09 C; 2.5-4 Si; 0.027-0.17 Mn; 0.007-0.02 S; 0.01-0.03 Al; 0.004-0.012 N; 0.06-5 Cu; balance Fe and impurities. The concast slab or strip is reheated to 1200-1300 deg. C before being hot rolled to a thickness of 1-5 mm and then coiled at 500-700 deg. C. The strip is then cold rolled to below 0.5 mm, annealed to produce a primary recrystallisation and a decarburisation in a moist atmosphere and then coated with MgO. Finally it is annealed to produce a secondary recrystallisation and coated with an insulation layer which is fired.

Description

(57)

A method for producing a crystal oriented electrical steel sheet, in particular for producing a transformer magnetic circuit, comprising continuous casting of steel onto a slab or steel strip containing less than 0.1% carbon, 2.5 to 4% silicon, and at least aluminum, nitrogen, manganese, sulfur and copper to form precipitates inhibiting normal growth, heating the slab or strip, hot-rolling the slab or strip to a thickness of 1 to 5 mm, rolling the hot-rolled sheet, annealing the hot-rolled sheet, cold rolling to final thickness less than 0.5 mm, primary recrystallization and decarburization annealing in a humid atmosphere, deposition of MgO on at least one side of the decarburized steel, final secondary recrystallization and purification annealing, application of an insulating coating and final calcination annealing of the coating, obtaining a slab or belt

A method of producing electrical crystal steel sheet, especially for trans

Technical field

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a process for the manufacture of an electrical steel sheet with oriented crystals, in particular for the manufacture of transformer magnetic circuits, comprising the steps of:

- continuous casting of steel in the form of a slab or strip of steel, containing, in particular, less than 0.1% carbon, 2.5 to 4% silicon and at least aluminum, nitrogen, manganese, sulfur, copper to form compounds inhibiting normal grow,

- heating of slab or strip,

- hot rolling of slabs or strips to obtain sheet thickness between 1 and 5 mm,

- hot rolling of rolled sheet,

- annealing of rolled sheet,

- cold rolling to a final thickness of less than 0,5 mm,

- primary recrystallization annealing and decarburization in a humid atmosphere,

- depositing MgO on at least one side of the decarburized sheet,

- final secondary recrystallization and purification annealing,

- applying an insulating coating and finally firing the coating by annealing.

BACKGROUND OF THE INVENTION

The texture of the oriented crystal steel sheet is the so-called Goss texture, symbolically expressed using Miller indices such as {110} <001>, where the axis <001>; which is the axis of easy magnetization, is approximately parallel to the rolling direction, and the plane {110} is a plane approximately parallel to the steel surface. This texture gives the crystal-oriented electrical steel sheet good magnetic properties in a rolling direction that is approximately easy to magnetize. Measurement of B800 induction, obtained at a magnetic field of 800 A / m, and energy losses W (1.7 / 50) in the steel sheet for In practice, a 1.7 Tesla (T) induction at a frequency of 50 Hz is used in practice to evaluate the magnetic quality of samples taken parallel to the sheet rolling direction.

Two types of oriented crystal sheets are commercially available:

- so-called conventional sheets are characterized by an induction of B800 of less than 1.86 T and are obtained by a process comprising in particular two cold rolling operations separated by annealing, the reduction ratio of the second rolling being generally less than 7%, so-called high throughput sheets are characterized with an induction of B800 greater than 1,88 T and obtained by a process comprising in particular one cold rolling operation or two cold rolling operations with intermediate annealing, the reduction ratio of the cold rolling in a single operation or the second cold rolling being generally higher than 80 %.

Prior to hot rolling, steel for conventional metal sheets contains manganese, sulfur and copper. High-permeability sheet steel contains aluminum, manganese, copper, sulfur and nitrogen before hot rolling.

There is known a process for producing a high-permeability orientated steel sheet having approximately texture (110} <001>, wherein the steel comprises aluminum, manganese, copper, sulfur and nitrogen. The aluminum combines with nitrogen to form aluminum nitride AlN and manganese and copper. The aluminum nitride, manganese sulphide and copper sulphide precipitates the normal growth of primary crystals during static texture annealing, while at the same time allowing the development of secondary recrystallization crystals having the desired Goss texture.

Heating of the steel slab prior to hot rolling is carried out in a known manner to a temperature above 1300 ° C, of the order of about 1350 to 1400 ° C, in order to allow a complete transition of the AlN, MnS and CuS precipitates alone or in combination into solution. In the cast state, their size, generally greater than 1 μπι, is too coarse to allow the development of secondary recrystallization. The AlN, MnS and CuS compounds, either alone or in combination, re-precipitate in the form of fine particles with an average size of less than 150 nm during hot rolling and annealing operations performed in a single operation before cold rolling.

The main disadvantage of heating a slab or steel-oriented steel strip to a temperature higher than 1300 ° C is the formation of liquid oxides, which requires periodically stopping the furnace specially adapted for this production for slagging.

To obtain a magnetic quality equivalent to products obtained using slab heating in the temperature range of 1350 to 1400 ° C, several metallurgical processes have been proposed using slab heating to below 1300 ° C.

For example, after hot rolling and decarburization, nitriding is used to form fine precipitates of silicon nitride and aluminum (Si, Al) N prior to the start of secondary recrystallization. The nitriding is carried out either by an additional heat treatment in a gaseous atmosphere containing ammonia NH ₃ or by the addition of nitrogen compounds such as manganese nitride MnN, ferromanganese nitride FeMnN and chromium nitride CrN to a shredder consisting mainly of MgO. The slabs generally contain aluminum and optionally titanium Ti, chromium Cr and boron B, which are elements known for their ability to form TiN, CrN and BN nitrides. Since this process aims to precipitate fine (Si, Al) N particles in the secondary recrystallization annealing stage, the earlier presence of fine MnS and AlN precipitates is not necessary.

As a result, the transition of large MnS and AlN precipitates into solution during slab heating prior to hot rolling is incomplete. In addition, an incomplete transition of aluminum into solution is necessary for the precipitation of silicon nitride.

Patents including

DE 4,311,151 and EP

619,376 disclose a process, heating slabs to a temperature, manganese sulfide solubility, copper sulfide solubility.

which is lower than but higher than temperature

Under these conditions, the copper sulfide precipitates dissolve. Conversely, manganese sulphide precipitates do not dissolve and, since they are in the form of coarse particles, no longer act as an inhibitor.

- Due to the precipitation of more than 60% nitrogen in the form of coarse AlN particles during hot rolling, the aluminum nitride precipitates also no longer act as an inhibitor.

In the process described in these documents, a necessary inhibitor of fine sulfide particles is formed by CuS, which precipitates during the annealing of the hot-rolled sheet.

SUMMARY OF THE INVENTION

The object of the present invention is a method for producing a crystal-oriented electrical sheet, in particular for the production of transformer magnetic circuits, the principle of which is that a steel having a mass composition

- 0.02 to 0.09% carbon,

- 2,5 to 4% silicon,

- 0,027 to 0,17% of manganese,

- 0,007 to 0,020% of sulfur,

- 0.010 to 0.030% aluminum,

- 0,004 to 0,012% of nitrogen,

- 0,06 to 0,50% of copper, the remainder being iron and impurities, subjected to continuous casting after slab or sheet formation

- heating to a temperature greater than 1200 ° C and less than or equal to 1300 ° C followed by hot rolling and rolling of the sheet obtained by hot rolling at a temperature between 500 and 700 ° C.

Further features of the invention are that:

- the strip is decarburized so that the oxygen content of the formed oxide film is less than 800.10%,

- the composition further contains up to 0,15% tin,

- the product of the sulfur content multiplied by the manganese content is less than 160.10 ^'5,

- the product of the nitrogen content multiplied by the aluminum content is less than 240 × ^{10 6} ,

- the steel is hot rolled to precipitate nitrogen in the form of fine particles, mainly containing nitrogen and aluminum, with an average diameter of less than 100 nm, the percentage of precipitated nitrogen being less than 40%,

- hot-rolled steel is annealed to precipitate nitrogen in the form of fine particles, mainly containing nitrogen and aluminum, with a mean diameter of less than 100 nm, the percentage of precipitated nitrogen being greater than 60%,

- steel is hot rolled to precipitate sulfur in the form of particles with a mean diameter of less than 100 nm,

after annealing, the hot - rolled sheet at a temperature between 850 and 1150 ° C for 1 to 10 minutes and cooling at a rate greater than 10 ° C / s from 800 ° C is carried out by cold rolling. a final thickness of less than 0,5 mm in one operation involving several passes, with an overall reduction ratio of more than 70%, the sheet temperature being at least one cold rolling pass between 100 and 300 ° C,

- cold rolling to a final thickness of less than 0.5 mm is carried out in two intermediate annealing operations at a temperature between 850 and 1150 ° C for 1 to 10 min, followed by the first step. cooling at a rate greater than 10 ° C / s to 800 ° C, wherein the reduction ratio of the second cold rolling operation is greater than 40% and the sheet temperature for at least one cold rolling pass is between 100 and 300 ° C if the reduction ratio is second cold rolling operations greater than 70%,

- prior to cold rolling in two operations, the sheet is annealed for 1 to 10 minutes at a temperature between 850 and 1150 ° C, in particular if the final sheet thickness is less than 0,27 mm,

- the magnesium oxide contains, in addition to the possible additions of titanium dioxide, boron or boron compound, at least one sulfur compound and / or a compound containing simultaneously sulfur and nitrogen and / or an antimony compound, taken alone or in combination,

- magnesium oxide contains, in addition to any additions of titanium dioxide, boron or boron compound, sulfur or one or more sulfur or nitrogen compounds selected from the group consisting of magnesium sulphate, manganese sulphate, urea and sodium thiosulphate,

- the magnesium oxide contains, in addition to any additions of titanium dioxide, boron or boron compound, at least one compound containing simultaneously sulfur and nitrogen selected from the group consisting of ammonium sulphate, sulphamic acid and ammonium thiosulphate,

- magnesium oxide contains antimony trichloride, in addition to any additions of titanium dioxide, boron or boron compound.

The invention relates to the use of steel having the following weight composition: 0.02 to 0.09% carbon, 2.5 to 4% silicon, 0.06 to 0.50% copper, and a choice between 0.027 and 0.17% manganese, 0.007 to 0.020% of sulfur, 0.010 to 0.030% of aluminum and 0.004 to 0.012% of nitrogen, the remainder being iron and impurities, the composition being heated to less than or equal to 1300 ° C after continuous slab or strip formation. According to the invention, there is no longer formation of surface oxides melting below this temperature, as shown in FIG. 1, for a total slab heating time of 4 h 30 min, the residence time at the intended heating temperature being 1 h. ° C, so that the precipitates of AlN, MnS and CuS, considered alone or in combination, can pass into solution in a sufficient quantity during heating of the slab, allowing secondary recrystallization and achieving favorable magnetic properties.

According to the invention, the content of manganese, sulfur, aluminum and nitrogen is selected within a very narrow range, allowing virtually complete transition of the AlN, MnS and CuS precipitates, considered alone or in combination, into solution during heating of slabs before hot rolling to a temperature equal to or less than 1300 ° C, which prevents the formation of fusible oxides on the surface.

According to the invention, the precipitates containing sulfur and / or nitrogen have largely gone into solution during heating of the slabs as a result of adjusting the chemical composition to a lower heating temperature The main inhibitor is aluminum nitride which precipitates little during hot rolling and primarily during sheet annealing hot rolled in the form of fine particles with an average diameter of less than 100 nm. Manganese sulphide is a complementary inhibitor. In particular, copper has a cleaning effect on the size of those AlN and MnS precipitates with which it can be combined. CuS precipitates, which trap some sulfur in the steel at the hot-rolling stage, contribute to reducing the mean diameter of the precipitates, as shown in Figure 2. These CuS precipitates, which are present in small amounts after annealing the hot-rolled sheet compared to the AlN precipitates , they pass into solution during the temperature rise during secondary recrystallization annealing. Thus, they do not participate significantly in the inhibition. The addition of one or more sulfur and / or nitrogen compounds to the magnesium oxide with which the sheet is coated with pb decarburization increases the inhibition by AlN and MnS.

The oriented crystal steel sheets of the invention are produced by a process comprising the following steps:

- continuous casting of steel in slabs between 150 and 300 mm thick,

- heating of slabs at a temperature between 1200 and 1300 ° C,

- hot rolling to a thickness of between 1 and 5 mm,

- rolling of hot-rolled sheet at 500 to 700 ° C,

- annealing the hot-rolled sheet at a temperature between 850 and 1150 ° C for 1 to 10 min followed by cooling at a rate greater than 10 ° C / s from 800 ° C,

- cold rolling to a final thickness of less than 0.5 mm in one operation, comprising several phases, with an overall reduction ratio of more than 70%, the sheet temperature being at least one cold rolling operation between 100 and 300 ° C,

- or cold rolling to a final thickness of less than 0,5 mm in two intermediate annealing operations carried out at a temperature between 850 and 1150 ° C for 1 to 10 min, followed by cooling from 800 ° C at a rate greater than 10 ° C / s, wherein the reduction ratio of the second cold rolling is greater than 40% and the sheet temperature is between 100 and 300 ° C during at least one pass if the total reduction ratio of the second cold rolling is greater than 70%.

In the case of two cold rolling operations with intermediate annealing, a possible short annealing for 1 to 10 min between 850 and 1150 ° C prior to the first cold rolling is capable of stabilizing by secondary recrystallization, particularly if the final sheet thickness is less than 0.27 mm; the cooling rate may be slower.

- primary recrystallization and decarburization annealing in a humid atmosphere containing hydrogen and nitrogen to the final thickness,

applying an anti-sticking agent consisting predominantly of magnesium oxide to at least one side of the sheet, the final secondary recrystallization and cleaning annealing of the metal, the application of the insulating coating and the final firing of the coating.

The oriented crystal steel according to the invention, which has been subjected to the production steps described above, contains 0.02 to 0.09% carbon, 2.5 to 4% silicon, 0.027 to 0.17% manganese, 0.007 to 0.020% sulfur, 0.010 to 0.030% aluminum, 0.004 to 0.012% nitrogen, 0.06 to 0.50% copper and optionally up to 0.15% tin, the remainder being iron and impurities.

The product of sulfur and manganese is less than or equal to 160.10 ' ⁵ :

(% S) x (% Mn) <160.10 ⁵

The product of nitrogen and aluminum is less than 240.10 ⁶ :

(% N) x (% Al) <240.10 ^-6

The percentage of nitrogen precipitated after hot rolling in the form of fine particles with an average diameter of less than 100 nm is less than 40%.

The percentage of nitrogen precipitated after hot rolling and calcination in the form of fine particles with a mean diameter of less than 100 nm is greater than 60%.

The magnesium oxide used as a separator for secondary recrystallization and purification annealing may contain, singly or in a mixture, sulfur or one or more sulfur or nitrogen compounds selected from the group consisting of magnesium sulfate and / or manganese sulfate and / or sodium thiosulfate and / or urea , one or more compounds simultaneously containing sulfur and nitrogen selected from the group consisting of sulfamic acid and / or ammonium sulfate and / or ammonium thiosulfate, antimony trichloride, boron or boron compound and titanium dioxide.

Giant. 2 shows the relationship between the mean diameter of the precipitates and the percentage of sulfur in the steel after hot rolling when all the precipitates have gone almost completely into solution during slab heating. In order to achieve a fine precipitation after hot rolling, the sulfur content of the invention is limited to 0.020%.

Since fine MnS precipitates play an active role as a secondary inhibitor during secondary recrystallization annealing, the sulfur content must be at least 0.007% to obtain a sufficient amount of these precipitates.

The manganese content of the invention must be greater than 0.027% in order to precipitate a sufficient amount of fine MnS precipitates exhibiting an inhibitory effect and to obtain free manganese that would be available if sulfur was added as an additive to magnesium oxide to increase the inhibitory ability of the MnS precipitates. It is limited to 0.17% to prevent coarse precipitation of MnS in slabs and its incomplete transition into solution during heating to 1200 to 1300 ° C before hot rolling.

According to the invention the presence of fine precipitates of MnS in slabs and their transition into the solution between 1200 and 1300 ° C before hot rolling favored in the condition [% S] x [% Mn] <160.10 * ^5.

In the process according to the invention the nitrogen content must be greater than

0.004% to achieve sufficient precipitation of fine precipitates of AlN, the main inhibitor, during annealing of the hot-rolled sheet. The nitrogen content is limited to 0.012% to prevent blistering on the steel surface. Condition (% N) × (% Al) <240.10 ^'6 enables virtually complete transition AlN precipitates into solution during slab heating between 1200 and 1300 ° C before hot rolling.

According to the invention, the aluminum content must be equal to or greater than

0.010%, on the one hand, that the amount of AlN precipitates formed during the annealing of the hot-rolled sheet is sufficient, with AlN being the main inhibitor, and, on the other hand, that free aluminum is available when nitrogen is added as an additive to magnesium oxide for increasing the inhibitory capacity of AlN precipitates. The aluminum content is less than 0.030% to avoid coagulation of coarse AlN particles during the final hot rolling phase.

In addition to the above elements, the steel may contain up to 0.15% tin, which has a beneficial effect on inhibition.

In the process of the invention, in which a lower sulfur and aluminum content is used than when heating slabs at a higher temperature, the density of inhibitor precipitates containing either sulfur and manganese or nitrogen and aluminum may prove insufficient to achieve complete secondary recrystallization and homogeneity magnetickýc

In seconds of properties in order to increase the stability of the recrystallization and thus avoid the scattering of the magnetic property values, it is preferable to add to the magnesium oxide one or more compounds containing sulfur and / or nitrogen or antimony which allow additional inhibitors, either sulfur and manganese or nitrogen based and aluminum or antimony-based, during the temperature increase prior to initiating secondary recrystallization.

BRIEF DESCRIPTION OF THE DRAWINGS

Giant. 1 is a curve showing weight loss versus slab heating temperature and formation of oxides melting above 1300 ° C.

Giant. 2 shows the relationship between the mean precipitate diameter and the percentage of sulfur in steel after hot rolling.

Giant. 3 shows the density of the precipitates after decarburization as a function of the secondary recrystallization annealing stopping temperature.

Giant. 4 shows the magnetic properties achieved according to the invention in the case of a cold rolling operation consisting of several passes, where the final thickness is 0.285 mm and corresponds to an overall reduction ratio of 87%.

Giant. 5A and 5B illustrate the magnetic properties achieved according to the invention as a function of the oxygen content of the surface film formed during decarburization of a 0.285 mm thick sheet which has been subjected to cold rolling with a reduction ratio of 87% to magnesium oxide applied to the sheet before by secondary recrystallization annealing, 1% sulfur was added as the sulfamic acid.

DETAILED DESCRIPTION OF THE INVENTION

The invention is illustrated by the following examples and findings. Table 1 shows the chemical composition of the steels tested. Steels 2 to 5 and 7 to 9 are steels according to the invention. According to the invention, the phosphorus content of the residual element is less than 0.015%.

Steel No 1 is a reference steel containing 0.021% sulfur and

0.030% of aluminum (No. 1 steel, Table 1) whose slab was heated to 1400 ° C prior to hot rolling to dissolve most of the coarse-grained AlN, MnS and CuS precipitates. The cold rolling was carried out according to the invention in one operation after annealing the hot-rolled sheet at 1120 ° C. Magnetic properties obtained at a final thickness of 0.285 mm:

W (1.7 / 50) = 1.03 watt / kg; B800 = 1.91 T

Under the same conditions, but at a temperature of annealing the steel slab no. 1 1280 C, magnetic properties are obtained at a thickness of 0.285 mm mediocre, because the product of the percentage of sulfur content and the percentage of the manganese content is greater than 160.10 ^'5:

W (1.7 / 50) = 1.65 watt / kg; B800 = 1.72 T

In the following examples, steel sheets were produced in the following manner:

- continuous casting of steel slabs 210 mm thick,

- slab heating at a temperature between 1200 and 1300 ° C with a temperature rise for 3 h 30 min and a delay at the desired temperature for 1 h, pre-hot rolling in 5 passes up to 45 mm thickness, finishing hot rolling in 7 passes n is a thickness of 2.3 mm, the starting temperature of the hot rolling being between 1070 and 1000 ° C and the final temperature between 965 and 915 ° C,

- rolling of hot-rolled sheet at 530 or 640 ° C,

- annealing the hot-rolled sheet with a temperature rise for approximately 60 s, a dwell at 950 ° C for 160 s and cooling the hot-rolled sheet, the transition time from

700 ° C to 300 ° C is less than 15 s, cold rolling to a final thickness in 6 passes, corresponding to successive cold reduction ratios of approximately 30%, with a rolling temperature of 230 ° C in the third pass (for Examples 2 to 9) ,

recrystallization and decarburization in a humid N ₂ / H ₂ atmosphere between 800 and 850 ° C, the heat treatment time being less than 500 s, the coating of the sheet with magnesium hydroxide slurry and drying; the magnesium hydroxide suspension consists of 150 g MgO per liter of water. Additives are added to this suspension. The percentage of element (Ti, B, S, Sb, Ν) added to the magnesium hydroxide is the mass of the element divided by the mass of dry magnesium oxide and multiplied by 100;

- slow secondary recrystallization annealing with a temperature rise of 15 ° C / h in an atmosphere of 25% N ₂ /75% H ₂ between 650 and 1200 ° C and the purification of the metal under hydrogen at 1200 ° C,

- applying an insulating coating and firing the coating; the coating consists of silica, aluminum phosphate and chromic acid.

Example 1

After heating the slab at 1280 ° C, hot rolling and rolling the sheet at 530 ° C, steel No. 2 was cold rolled to an intermediate thickness of 0.74 mm, annealed for 90 s at 1050 ° C, then cooled very quickly from 800 ° C, the transition time from 700 to 300 ° C being less than 15 s, and then rolled to a final thickness of 0.285 mm, corresponding to a second cold reduction ratio of 61%. After further processing as described above, the magnetic properties are achieved:

losses (1.7 / 50) 1.27 W / kg B800 1.85 T

Example 2

After heating the slab to 1280 ° C, hot rolling and rolling at 530 ° C, annealing the hot rolled sheet for 160 s at 950 ° C, very fast cooling from 800 ° C, cold rolling to a final thickness of 0.285 mm, which corresponds to a cold reduction ratio of 87%, and by further processing as described above, the magnetic properties for steel No. 3 are achieved:

losses (1,7 / 50) B800

1.03 W / kg 1.93 T

According to these two examples, it appears that the reduction ratio of the final cold rolling must be greater than 70% to obtain the best magnetic properties.

In Examples 1 and 2, the annealing separator consisted of magnesium oxide containing 0.080% boron and 1.2% titanium element TiO ₂ .

Example 3

Under the conditions of Example 2,% sulfur was added to the magnesium oxide in the form of ammonium sulfate. For steel No 2, the following magnetic properties are obtained:

without addition of (NH ₄ ) ₂ SO ₄ with addition of 10% (NH ₄ ) ₂ SO ₄

B800

1,89 T

1,94 T

Example 4

Under the conditions of Example 2, 3% by weight of sulfur in the form of magnesium sulfate was added to the magnesium oxide. Magnetic properties obtained for steel No 2:

losses (1.7 / 50) 1.02 W / kg

B800 1.94 T

Example 5

Under the conditions of Example 2, 1% sulfur in the form of sulfamic acid was added to the magnesium oxide. Magnetic properties obtained for steel No 2:

losses (1.7 / 50) 1.01 W / kg

B800 1.94 T

Example 6

Under the conditions of Example 2, 0.026% of the antimony element in the form of antimony trichloride was added to the magnesium oxide. Magnetic properties obtained for steel No 2:

loss (1.7 / 50) 1.03 W / kg

B800

1,92 T

Example 7

Under the conditions of Example 2, with a annealing temperature of 1050 ° C hot-rolled sheet, 0.93% nitrogen in the form of urea was added to the magnesium oxide. Properties obtained for steel No 7:

loss (1.7 / 50) 1.06 W / kg

B800 1.91 T

Example 8

Under the conditions of Example 2, but with the annealing temperature of the hot-rolled sheet of 1080 ° C and using magnesium oxide containing 3.6% titanium in the form of titanium dioxide, 0.10% boron and free of sulfur and / or nitrogen additives and antimony trichloride are Properties obtained for steel No 8:

loss (1.7 / 50) 0.98 W / kg

B800 1.93 T

Example 9

Under the conditions of Example 2, but with a slab heating temperature of 1240 ° C, a annealing temperature of the hot-rolled sheet of 1050 ° C and using magnesium oxide containing 1.5% sulfur in the form of sulfamic acid, the magnetic properties obtained for steel No. 9 are obtained:

losses (1,7 / 50)

B800

1.03 W / kg 1.92 T

The addition of sulfur or a sulfur compound (magnesium sulfate, manganese sulfate or sodium thiosulfate) to magnesium oxide increases the inhibition of manganese and sulfur containing precipitates during secondary recrystallization annealing.

The addition of a nitrogen (urea) compound to magnesium oxide allows the introduction of nitrogen into the steel, which increases the inhibition of nitrogen and aluminum containing precipitates.

The addition of a sulfur and nitrogen containing compound (ammonium thiosulfate or sulfamic acid, which simultaneously contains 33% sulfur and 14% nitrogen) makes it possible to simultaneously introduce sulfur and nitrogen into the steel to increase inhibition by precipitates containing both manganese and sulfur and nitrogen and aluminum. If sulfur and nitrogen diffuse into the steel, it will additionally precipitate very fine inhibitory particles before the secondary recrystallization begins.

The beneficial effect of nitrogen in conjunction with sulfur is illustrated by the fact that the percentage of sulfur used in Example 5 is less than that of Example 4.

The addition of ammonium sulfate to magnesium oxide also allows the simultaneous addition of sulfur and nitrogen. The addition of antimony trichloride to magnesium oxide makes it possible to introduce an element of antimony into the steel which segregates at the crystal boundaries and thus acts as an inhibitor. The addition of a water-soluble sulfur compound is preferable to the optional addition of insoluble elemental sulfur, since the dispersion in magnesium hydroxide is then more homogeneous. The addition of sulfur, nitrogen, and antimony containing compounds to the magnesium oxide promotes a homogeneous magnetic character along the length of the coil sheet.

Table 2 shows that according to the invention the percentage of nitrogen precipitated in the hot-rolled sheet is less than 40

%. The lowering of the coiling temperature makes it possible to significantly reduce the percentage of precipitated nitrogen to less than 5% in the case of steel No. 3, subjected to heating to 1280 ° C, hot rolled and coiled at 530 ° C. At this coiling temperature, the percentage of precipitated nitrogen remains very low if the slab heating temperature is lowered from 1280 to 1240 ° C, ie. the usual heating temperature of carbon steels.

In general, lowering the coiling temperature below 600 ° C avoids precipitation of coarse particles that do not exhibit an inhibitory effect.

The amount of nitrogen combined with aluminum was determined by quantitative analysis of the precipitated aluminum. By heating slabs between 1200 and 1300 ° C according to the invention, a low percentage of nitrogen precipitated in the hot rolled state can be achieved by strictly controlling the Mn, S, Al and N content, which does not allow higher contents characterizing the known way of heating slabs to higher temperatures. 1350 ° C.

Table 3 shows that, according to the invention, after annealing the hot-rolled sheet at 950 ° C, the percentage of precipitated nitrogen is greater than 60%.

Table 4 shows that, according to the invention, the mean diameter of the nitrogen and aluminum containing precipitates obtained by annealing a hot rolled steel sheet No. 2 for 160 s and rolling at 530 ° C over a wide range of annealing temperatures is less than 50 nm .

Thus, nitrogen and aluminum containing precipitates are able to play an active role as inhibitors.

The influence of copper was analyzed within the scope of the invention.

Table 5 shows the mean diameter and density of the precipitates after heating the No. 2 steel slab containing 0.15% copper to 128 ° C, hot rolling to a thickness of 2.3 mm, and rolling at 640 ° C.

For comparison, the properties of precipitates in reference steel sheet No. 1, containing 0.09% copper, are hot rolled to a thickness of 2.3 mm and rolled at 640 ° C. It can be seen from Table 5 that an increase in the copper content leads to an increase in the density of CuS and AlNCuS precipitates and a decrease in their mean diameter. Combinations of precipitated compounds are labeled with the constituent elements, regardless of their relative proportions.

In the steel sheet 2 in the raw state after hot rolling, most of the CuS and AlNCuS particles have a small diameter and the manganese-containing particles are minor. The addition of copper and copper sulfur capture makes it possible to avoid the formation of coarse manganese-containing particles that are too large in diameter to act as an inhibitor during hot rolling. The study of Table 4 shows a decrease in the number of copper-containing particles when the annealing temperature of the hot-rolled sheet increases, indicating a partial dissolution of the Al, N, Cu, S-containing particles.

Giant. 3 shows changes in the density of CuS and MnCuS precipitates after decarburization and during secondary recrystallization annealing of non-aluminum steel No. 6, which composition is selected to facilitate precipitate reading by transmission electron microscopy. This steel, whose slabs were subjected to heating at 1400 ° C, was subjected to two cold rolling operations with an annealing at 950 ° C, with a reduction ratio of the second cold rolling being 60%.

Fine CuS precipitates dissolve progressively prior to secondary recrystallization, which occurs at about 950 ° C, with sulfur release accompanied by fine precipitation of particles

MnS. The particles identified in an electron microscope are

MnCuS because copper cools on the MnS particles during cooling.

to 9 is

According to the invention, fine CuS particles do not play a decisive role as an inhibitor for the development of secondary recrystallization.

In steel # 2, the percentage of CuS precipitates with a mean diameter less than 100 nm is less than 3% of the total population after annealing of the hot-rolled sheet. It is precisely the MnS precipitates formed after decarburization and before secondary recrystallization that they promote by inhibition through nitrogen and aluminum containing precipitates.

According to the invention, the copper content must be greater than 0.06% in order to obtain a fine precipitation in the hot-rolled and hot-rolled and annealed stages. Increasing the copper content leads to a refinement of the precipitates. The copper content is limited to 0.50% to avoid pickling problems of the sheets obtained.

As demonstrated in the examples, by heating slabs to a temperature greater than 1200 ° C and equal to or less than 1300 ° C, crystal-oriented electrical steel sheets having either the magnetic properties of conventional sheets (B800 <1.86 T) can be produced, using two cold rolling operations, separated by annealing, with a second cold rolling reduction ratio ranging from 40 to 70%, or the magnetic properties of high-throughput sheets (B800> 1,88 T) using a single cold rolling operation, prior to which is preceded by annealing or two cold rolling operations separated by annealing, the reduction ratio in the final cold rolling being greater than 70%. Lowering the heating temperature over the known process makes it possible to avoid the formation of liquid oxides that clog the furnace.

In the case of final cold rolling with a reduction ratio of more than 40% as shown in Figure 4, either the magnetic properties of conventional sheets (B800 <

1.86 T) or magnetic properties of high permeability sheets (B800> 1.88 T).

It has been observed, as shown in Fig. 5, that the level of loss decreases and the B800 value increases as a function of the reduction in the oxygen content by weight of the surface film formed during the decarburization operation. Reducing the oxygen content of the surface oxide film consisting mainly of silicon dioxide, and containing less than 20% of iron oxide, under 800.10 ^'4% (about 1.8 g of oxygen per m ²⁾ enables the improvement of the magnetic properties more pronounced the greater the reduction is .

The process of the invention, described for continuous cast slabs having a thickness of between 150 and 300 mm, can also be applied to thinner slabs with a thickness of between approximately 15 and 100 mm.

The process according to the invention can also be applied to a thin strip obtained by casting steel between two rolls with a thickness greater than 2 mm, the strip being subjected to heating between 1200 and 1300 ° C prior to hot rolling.

The number of pre-hot and post-hot passes passes depends on the thickness of the continuously cast product and the intended thickness after hot rolling. If the thickness of the continuously cast product is sufficiently small, pre-hot rolling may be omitted.

The total heating cycle time for a continuously cast product depends on its thickness. The smaller this thickness, the faster the core heats up.

Table 1. Chemical analysis (mass percent) of slabs

steel marking Si C Mn WITH Al N Cu Sn 1 3.16 0,060 0,081 0,021 0.030 0.0074 0.09 <0.015 2 3.15 0,044 0,080 0.011 0,025 0.0086 0.151 <0.015 3 3.18 0.057 0,081 0.015 0,021 0.0072 0.154 <0.015 .4 3.16 0,059 0,079 0.014 0,026 0,0073 0.150 <0.015 5 3.15 0,058 0,079 0.012 0,021 0.0093 0.151 <0.015 6 3.21 0,042 0,058 0.020 0.001 0,0042 0.205 <0.015 7 3.12 0,058 0,080 0.015 0.024 0.0074 0.149 <0.015 8 3.26 0,054 0,079 0.015 0.019 0.0066 0.010 0,069 9 3.12 0,056 0,078 0.011 0.019 0.0068 0.014 <0.015

Table 2. Percentage of precipitated nitrogen after hot rolling

steel marking temperature of slab heating (° C) coiling temperature (° C) % precipitated N 1 1400 640 40 2 1280 530 21 3 1280 640 530 24 3 4 1280 640 530 37 12 5 1245 640 34 8 1240 530 12 1280 530 7 9 1240 530 9 1280 530 3

Table 3. Percentage of nitrogen precipitated after annealing of hot-rolled sheet

steel marking temperature of slab heating (° C) coiling temperature (° C) % precipitated N 2 1280 530 75 3 1280 640 530 74 75 4 1280 640 530 77 82

Table 4. Effect of annealing temperature of hot-rolled sheet on mean diameter, density and nature of aluminum-containing precipitates

annealing temperature (° C) mean diameter (nm) standard deviation (nm) density (number / pm ² ) character precipitates 900 27.05 14.59 13.2 AlNCuS steel No. 2 950 29.02 17.18 9.0 AlN a AlNCuS 1000 32.49 20.49 7.3 mostly AlN steel No. 1 1120 38.8 25.1 7.5 AlN a AlNCuS

Table 5. Characteristics of precipitates after hot rolling (before annealing)

Hi MnCUS MnS AlNCuS AlNMnCuS AlNMnS total steel no. 1 medium diameter (nm) 87.3 141.5 64.7 102.4 104.3 density (number / pm ² ) 0.178 0.474 0 0.346 0.272 0 1,269

steel no. 2 medium diameter (nm) 69.4 143.1 85.8 45.9 77.0 70.9 62.3 density (number / pm ² ) 0.355 0,079 0.015 0,686 0.138 0.010 1,285

η

Claims (5)

PATENTOVÉ ! I3Í OJ. > < O O rc : γ ' LO ' czx r— O > &. 1 ⁵ 5! cn rc rj CLAIMS 1. A method for producing a crystal oriented electrical steel sheet, in particular for manufacturing a transformer magnetic circuit, comprising sequentially - continuous casting of steel in the form of a slab or strip of steel, containing by weight, in particular, less than 0.1% of carbon, 2.5 to 4% of silicon and at least aluminum, nitrogen, manganese, sulfur, copper to form precipitating inhibitors normal growth, - heating of the slab or strip, - hot rolling of slabs or strips to obtain sheet thickness between 1 and 5 mm, - hot rolling of rolled sheet, - annealing of hot-rolled sheet, - cold rolling to a final thickness of less than 0,5 mm, - primary recrystallization annealing and decarburization in a humid atmosphere, - depositing MgO on at least one side of decarburized steel, - final secondary recrystallization and purification annealing, - applying an insulating coating and final annealing the coating, characterized in that the steel composition by weight - 0.02 to 0.09% carbon, - 2,5 to 4% silicon, - 0,027 to 0.17 % Manganese, - 0,007 to 0.020 % open, - 0,010 in az 0.030 % aluminum, - 0,004 to 0.012 % nitrogen, - 0,06 to 0,50% of copper, the remainder being iron and impurities, subjected to continuous casting after slab or sheet formation - heating to a temperature greater than 1200 ° C and less than or equal to 1300 ° C and then, after obtaining the hot-rolled sheet, rolling the hot-rolled sheet at a temperature between 500 and 700 ° C. Method according to claim 1, characterized in that the strip is decarburized so that the oxygen content of the oxide film formed is less than 800 x ^{10 4} %. The method of claim 1, wherein the composition further comprises up to 0.15% tin. The method of claim 1, wherein the product of the sulfur content multiplied by the manganese content is less than 160 x ^{10 5} . The method of claim 1, wherein the product of the nitrogen content multiplied by the aluminum content is less than 240 x 10 6 ^s . less than 0.5 mm is carried out in two intermediate annealing operations at a temperature of between 850 and 1150 ° C for 1 to 10 min followed by cooling at a rate of greater than 10 ° C / s and 800 ° C, the reduction ratio of the second the cold is greater than 40% and the sheet temperature for at least one cold rolling pass is between 100 and 300 ° C if the reduction ratio of the second cold rolling operation is greater than 70%. Method according to claim 10, characterized in that, before the cold rolling in two operations, the sheet is annealed for 1 to 10 minutes at a temperature between 850 and 1150 ° C, in particular if the final sheet thickness is less than 0. , 27 mm. The method according to claims 1 to 11, characterized in that the magnesium oxide contains, in addition to optional additions of titanium dioxide, boron or boron compound, at least one sulfur or nitrogen-containing compound, sulfur-nitrogen-containing compound or antimony compound, considered alone or in combination. . The process according to claims 1 to 11, wherein the magnesium oxide contains, in addition to optional additions of titanium dioxide, boron or a boron compound, sulfur or one or more sulfur compounds selected from the group consisting of magnesium sulfate, manganese sulfate and sodium thiosulfate. Method according to claims 1 to 11, characterized in that the magnesium oxide contains, in addition to the optional additions of titanium dioxide, boron or boron compound, at least one sulfur and / or nitrogen-containing compound selected from