The present invention relates to a process for the production of grain-oriented electrical steel, to a grain-oriented steel strip prepared by the process, to a grain-oriented steel strip having a Peak Magnetic Polarization for the peak magnetic field strength of 800 A/m at 50 Hz of 1.85 to 1.98 T, and to the use in electric transformers, in electric motors or in electric devices, preferably where magnetic flux has to be channeled or contained.

Grain Oriented Electrical Steel (GOES) is a soft magnetic material preferably containing high silicon content providing high permeability to the magnetic field, easily magnetizing and demagnetizing. For example, GOES is the steel sheet used for manufacturing electric transformer cores with a minimum specific loss and a high achievable working induction, for example up to 1.85 T for a wide range of thicknesses like 0.23 to 0.35 mm.

According to Wuppermann et al., Electrical Steel, Stahl-Informations-Zentrum, Düsseldorf, Ed. 2005, pages 5 and 6, the iron crystal axis is an axis of easy magnetization of the body-centered cubic iron crystal. This axis, oriented closely to the rolling direction, gives excellent magnetic properties to the GOES in this direction of the steel strip. These are the orientation grains called "Goss grains" which provide a strongly anisotropic behaviour and reduce the power loss. The Goss texture makes it very difficult to orient the magnetic moments out of the plane of the sheet and in the direction perpendicular to the direction of rolling.

According to N. Chen et al., Acta Materialia 51 (2003), pages 1755 to 1765 and K. Günther et al., Journal of Magnetism and Magnetic Materials 320 (2008), 2411 to 2422 the manufacturing of GOES is in general performed according to different technologies across the world. To achieve the highly oriented Goss texture, the metallurgical process is highly complex and may consist in the following manufacturing steps: steel melting via a blast furnace and basic oxygen converter or an electric arc furnace, steel metallurgy refining via a vacuum degassing vessel, casting to slab via continuous casting or thin slab or thin strip, slab reheating or direct slab rolling on a hot rolling mill to get a hot rolled coil, coil surface preparation, hot strip annealing and pickling, cold rolling in one or two stages down to a final thickness, decarburization annealing and optionally a surface nitridation, providing a MgO coating of the strip surface, high temperature box annealing where the cold rolled decarburized coils are stacked, heat flattening and insulation coating and optionally a magnetic domain refinement.

According to the so called "High Heating" technology, the casting and the high temperature slab reheating conditions to about 1400 °C make it possible to have a well-developed inhibition system comprising particles of AIN, MnS and other compounds in the iron matrix, even before the cold process, which promotes abnormal grain growth. However, in low heating technology, with the low temperature in the slab heating process, the inhibition system is absent or weak, therefore low heating technology requires a nitridation treatment of the strip surface after the decarburization annealing stage to build a required inhibition system.

Therefore, the primary recrystallization (PRX), occurring during this decarburization anneal will control and prepare the secondary grain growth. However, due to the large number of metallurgical phenomena competing during this stage like carbon removal, formation of the oxide layer, primary grain growth, this process is unstable but fundamental for obtaining an efficient nitridation, a high-quality glass film, and many Goss germs in the matrix. Indeed it is known that a dense oxide layer, produced during the beginning of annealing, can be favorable to a good surface aspect, but may become a barrier to decarburization and nitration.

According to the prior art, the next metallurgical step is to hold the steel strip in a high temperature annealing cycle either in a batch annealing furnace or a rotary batch annealing furnace, where secondary recrystallization (SRX) occurs and where the main objectives are to develop abnormal grain growth to obtain a Goss texture with the inhibitors previously formed, to eliminate all elements as sulphur or nitrogen when SRX is finished and to form a coating layer named glass film containing Mg₂SiO₄ to ensure electric insulation and surface tension.

Problems that may occur with the processes according to the prior art are that all these mechanisms require thermal energy and time, in particular due to the large mass of coil to be heated in batch to allow diffusion and grain growth, which constitutes a high time and cost consumption in the current GOES manufacturing. In including safety steps and possible intermediate soakings the total process lead time lasts about 6 days. Moreover the coil windings require the use of a layer of MgO to isolate the steel surface and then avoiding the surface stickiness of the windings in the long and high temperature box annealing. Furthermore in a coil batch annealing, the thermic treatment is heterogeneous. At a certain time, the temperature is different at any strip position in width and length. In case of a continuous strip annealing treatment the temperature is homogenate and therefore the SRX strip temperature can be optimized and controlled.

As iron-silicon alloy is an electrical conductive media, induced currents develop over the sheet thickness under the effect of a magnetic flux variation over time; they are called the eddy currents. The reduction of the thickness as well as the increase of the electrical resistivity by addition of alloy elements as for example silicon, are the main two factors able to reduce significantly the losses induced by the eddy currents. Indeed a 10% thickness decrease results in a reduction by ca 20% in Eddy current losses at the same 50 Hz induction level. Whereas a 0.5% increase Silicon content results in a reduction by ca 12% in Eddy current losses at the same 50 Hz induction level. However, the issues in the conventional GOES manufacturing are that thinner thickness and more silicon content make the material more brittle, more difficult to cold roll and more difficult to reach a stable secondary recrystallization SRX particularly for material having a final thickness gauge lower than 0.22 mm.

The object of the present invention is therefore to provide an improved process for the preparation of grain oriented electrical steel which does not comprise the problems of the known processes as mentioned above, in particular SRX shall be optimized. Further, a more efficient way of handling energy during the production should be found and a new manufacturing method allowing to process thin GOES gauges with high silicon content except the known conventional cold processing treatment are wanted.

These objects are solved by the process according to the present invention for the production of grain-oriented electrical steel sheet at least comprising the following steps:

1. (A) providing a hot rolled steel strip based on a steel comprising, beside Fe and unavoidable impurities (all amounts are % by weight):
   • 1 to 8% Si,
   • less than 0.010% S + Se, and
   • less than 3% C + Mn + Cu + Cr + Sn + Al + N + Ti + B,
2. (B) at least one cold rolling step of the hot strip of step (A) to obtain a cold strip,
3. (C) a primary recrystallization annealing of the cold strip obtained in step (B) optionally including a nitriding treatment,
4. (D) a secondary recrystallization annealing treatment by heating to a temperature OTAG2 with a heating rate of at least 40 K/s to obtain the grain-oriented electrical steel sheet,

$$\mathrm{1420}\mathrm{K}-\mathrm{DP}\times \mathrm{PGS}\times \mathrm{\rho HAGB}/\log \left(\left(\mathrm{S}+\mathrm{\Delta N}\right)\times \mathrm{HRSRX}/\mathrm{20}\right)<\mathrm{OTAG}\mathrm{2}<\mathrm{1420}\mathrm{K}$$

OTAG2

Optimum Temperature of Abnormal Grain Growth in K,

HRSRX

Heating Rate to Secondary Recrystallization Treatment in K/s,

PGS

Average Primary Grain Size in µm,

ΔN

Nitriding Degree in ppm, calculated by Nitrogen Degree in ppm before SRX annealing (D) minus Nitrogen Degree in ppm before primary recrystallization annealing (C)

DP

Atmosphere Dew Point during heating rate in K,

S

sum of Sulphur content and Selenium content in ppm,

ρHAGB

High Angle (> 15°) primary Grain Boundary average density in µm^-1.

Unless explicitly stated otherwise, in the present text and the claims, the contents of particular alloy elements are each reported in % by weight.

The above mentioned objects are further solved by a grain-oriented steel strip prepared by the process according to the present invention, by a grain-oriented steel strip having a Peak Magnetic Polarization for the peak magnetic field strength of 800 A/m at 50 Hz of 1.85 to 1.98 T. and by the use of a steel strip according to the present invention in electric transformers, in electric motors or in any electric device where magnetic flux has to be channeled or contained.

The process according to the present invention and its single steps are explained in detail in the following:
Step (A) of the process according to the present invention comprises providing a hot rolled steel strip based on a steel comprising, beside Fe and unavoidable impurities (all amounts are % by weight) 1 to 8% Si, less than 0.010% S + Se, and less than 3% C + Mn + Cu + Cr + Sn + Al + N + Ti + B.

According to the present invention, the amount of Si present in the steel that is the basis of the hot rolled steel strip that is provided in step (A) is 1 to 8% Si, preferably 2 to 5% Si.

According to the present invention, the amount of C present in the steel that is the basis of the hot rolled steel strip that is provided in step (A) is preferably 0.001% to 1.0% C, particularly preferably 0.01% to 0.1% C.

According to the present invention, the amount of Mn present in the steel that is the basis of the hot rolled steel strip that is provided in step (A) is preferably 0.001% to 3.0% Mn, particularly preferably 0.01% to 0.3% Mn.

According to the present invention, the amount of S and Se present in the steel that is the basis of the hot rolled steel strip that is provided in step (A) is preferably 0.0001% to 0.01% S and Se, particularly preferably 0.001% to 0.01% S and Se.

According to the present invention, the amount of Cu present in the steel that is the basis of the hot rolled steel strip that is provided in step (A) is preferably 0.001% to 3.0% Cu, particularly preferably 0.01% to 0.3% Cu.

According to the present invention, the amount of Al present in the steel that is the basis of the hot rolled steel strip that is provided in step (A) is preferably 0.001% to 2.0% Al, particularly preferably 0.01% to 1.0% Al.

According to the present invention, the amount of N present in the steel that is the basis of the hot rolled steel strip that is provided in step (A) is preferably 0.0001% to 0.10% N, particularly preferably 0.001% to 0.01% N.

According to the present invention, the amount of Cr and Sn and Ti and B in sum present in the steel is less than 3%, particularly preferably less than 1%.

The present invention preferably relates to the process according to the present invention, wherein the hot rolled steel strip is based on a steel comprising, beside Fe and unavoidable impurities (all amounts are % by weight) 2 to 5 Si, 0.01 to 0.1 C, 0.01 to 0.3 Mn, 0.001 to 0.01 S, 0.01 t 0.3 Cu, 0.01 to 1.0 Al and 0.001 to 0.01 N.

In general, the step of providing a hot rolled steel strip based on a steel as defined above is known to the skilled artisan and is, for example, described in DE 19745455 C2 and EP 1752 549 B1.

In particular, step (A) of the process according to the present invention comprises a steelmaking to obtain a steel having the above mentioned composition. The step of steelmaking is also known to the skilled artisan and is described in the documents mentioned above. Afterwards the steel is preferably processed in a hot melt casting to obtain bars of steel. More preferably, the bars obtained accordingly are hot rolled into hot band strips which preferably undergo a hot strip annealing and pickling. The hot band strips that are obtained in step (A) of the process according to the present invention preferably have a thickness of 0.5 to 3.5 mm, more preferably 1.0 to 3.0 mm.

After step (A) hot band strips having the above mentioned composition and thickness are obtained. These hot band strips are preferably directly introduced into step (B) of the process according to the present invention.

Step (B) of the process according to the present invention comprises at least one cold rolling step of the hot strip of step (A) to obtain a cold strip. Cold rolling which is done in step (B) of the process according to the present invention is in general known to the skilled artisan and is, for example, described in WO 2007/014868 and WO 99/19521.

According to the present invention, in step (B) one, two or more cold rolling steps are conducted. Preferably, in step (B) of the process according to the present invention at least two cold rolling steps are conducted.

The present invention therefore preferably relates to the process according to the present invention, wherein in step (B) at least two cold rolling steps are conducted.

Further preferred, in step (B) of the process according to the present invention, a first cold rolling step is conducted, in which the hot rolled strip that is obtained from step (A) of the process according to the present invention is cold rolled down to a thickness of for example 0.05 to 2.00 mm, preferably 0.10 to 0.55 mm. Apparatuses in which cold rolling is conducted are in general known to the skilled artisan, for example mentioned in WO 2007/014868 and WO 99/19521.

Further preferred, the cold rolled strip that is obtained in this first cold rolling step is decarburized after the first cold rolling step. This can be done according to methods known to the skilled artisan, for example in an Intermediate Annealing stage at a temperature of 700 to 950 °C, preferably 800 to 900 °C. The Dew Point of the atmosphere which is present in this annealing stage can be 10 to 80 °C. Apparatuses in which this annealing is conducted are in general known to the skilled artisan, for example described in WO 2007/014868 and WO 99/19521. Annealing is preferably conducted to obtain a steel sheet or strip having a low carbon content, for example less than 30 ppm.

Preferably a pickling step is conducted after the annealing stage and the optional nitriding stage, which can be made according to methods known to the skilled artisan. For example, pickling can be conducted by using aqueous solutions of acids like phosphoric acid, sulfuric acid and/or hydrochloric acid. The present invention therefore preferably relates to the process according to the present invention, wherein a pickling step is conducted after step (C) and before step (D).

According to a preferred embodiment of the process according to the present invention, the steel sheet that is obtained after the first cold rolling step in step (B) of the process according to the present invention has a carbon content of less than 30 ppm before the final, preferably the second, cold rolling step in step (B).

The present invention therefore preferably relates to the process according to the present invention, wherein the steel sheet has a carbon content of less than 30 ppm before the final cold rolling step in step (B).

Further preferred, a second cold rolling step is conducted, in which the cold rolled strip obtained from the first cold rolling step, preferably after annealing and pickling, is further rolled down to a thickness of 0.05 to 0.35 mm, more preferably 0.10 to 0.22 mm.

The present invention preferably relates to the process according to the present invention, wherein the cold strip has a thickness of 0.05 to 0.35 mm, preferably 0.10 to 0.22 mm, after step (B).

Step (C) of the process according to the present invention comprises an annealing of the cold strip obtained in step (B) resulting in primary recrystallization and optionally a nitriding treatment.

This annealing is preferably conducted at a temperature of for example 400 to 950 °C, more preferably 600 to 900 °C. The optional nitriding treatment is further preferably conducted in an atmosphere comprising N₂ or N-comprising compounds, for example NH₃. Annealing and nitriding can be conducted separately in two successive steps, wherein annealing is conducted first. According to a second embodiment, annealing and nitriding can be conducted in one single step.

The annealing step (C) is preferably conducted to obtain a cold rolled strip having a nitriding degree, calculated by Nitrogen Degree in ppm before SRX annealing (D) minus Nitrogen Degree in ppm before primary recrystallization annealing (C), of 0 to 300 ppm, more preferably 20 to 250 ppm. Furthermore, the strip that is obtained after step (C) of the process according to the present invention has an average grain size of preferably 5 to 25µm, more preferably 5 to 20 pm. In addition, the strip that is obtained after step (C) of the process according to the present invention has preferably an average High Angle primary Grain Boundary density of 0.005 to 0.1 µm^-1, more preferably of 0.01 to 0.09 µm^-1.

Further details of step (C) of the process according to the present invention are known to the skilled artisan.

Step (D) of the process according to the present invention comprises a secondary recrystallization annealing treatment by heating to a temperature OTAG2 with a heating rate of at least 40 K/s to obtain the grain-oriented electrical steel sheet. According to the present invention, the temperature OTAG2 is set according to the following equation (I): $$\mathrm{1420}\mathrm{K}-\mathrm{DP}\times \mathrm{PGS}\times \mathrm{\rho HAGB}/\log \left(\left(\mathrm{S}+\mathrm{\Delta N}\right)\times \mathrm{HRSRX}/\mathrm{20}\right)<\mathrm{OTAG}\mathrm{2}<\mathrm{1420}\mathrm{K}$$ wherein OTAG2, HRSRX, PGS, ΔN, DP, S and ρHAGB have the following meanings:

OTAG2

Optimum Temperature of Abnormal Grain Growth in K,

HRSRX

Heating Rate to Secondary Recrystallization Treatment in K/s,

PGS

Average Primary Grain Size in µm,

ΔN

Nitriding Degree in ppm, calculated by Nitrogen Degree in ppm before SRX annealing (D) minus Nitrogen Degree in ppm before primary recrystallization annealing (C)

DP

Atmosphere Dew Point during heating rate in K,

S

sum of Sulphur content and Selenium content in ppm,

ρHAGB

High Angle (> 15°) primary Grain Boundary average density in µm^-1.

The inventor of the present invention have found that particularly advantageous grain-oriented electrical steel sheets are obtained, if a secondary annealing treatment is conducted at a certain temperature OTAG2, which depends on Heating Rate to Secondary Recrystallization Treatment (HRSRX) in K/s, the Average Primary Grain Size (PGS) in pm, the Nitriding Degree (ΔN) in ppm, the Atmosphere Dew Point during heating rate (DP) in K, the sum of Sulphur content and Selenium content (S) in ppm and the High Angle (> 15°) primary Grain Boundary average density (pHAGB) in µm^-1.

If the secondary recrystallization annealing treatment in step (D) of the process according to the present invention is conducted by heating to a temperature OTAG2 with a heating rate of at least 40 K/s, preferably at least 50 K/s, a grain oriented steel sheet is obtained having a high peak magnetic polarization for the peak magnetic field strength of 800 A/m and a low specific total loss.

According to the present invention, the upper limit of OTAG2 is preferably 1420 K, particularly preferably 1415 K.

According to the present invention, the Heating Rate to Secondary Recrystallization Treatment is preferably 20 to 800 K/s, more preferably 50 to 750 K/s. The Heating Rate to Secondary Recrystallization Treatment is acquired with methods known to the skilled artisan, for example as described in EP 2 486157.

According to the present invention, the Average Primary Grain Size is preferably 5 to 25 µm, more preferably 5 to 20 µm. The Average Primary Grain Size is acquired with methods known to the skilled artisan, for example Grain size measured by EBSD analysis (OIM Analysis software).

According to the present invention, the Nitriding Degree, calculated by Nitrogen Degree in ppm before SRX annealing (D) minus Nitrogen Degree in ppm before primary recrystallization annealing (C), is preferably 0 to 300 ppm, more preferably 20 to 250 ppm. The Nitriding Degree is acquired with methods known to the skilled artisan, for example Nitrogen Elemental Analyzer of A36 LECO Corporation.

According to the present invention, the Atmosphere Dew Point during heating rate is preferably 223 to 273 K, more preferably 243 to 270 K. The Atmosphere Dew Point is acquired with methods known to the skilled artisan, for example as described in WO 2007/014868 and WO 99/19521.

According to the present invention, the sum of Sulphur content and Selenium content is preferably 1 to 100 ppm, more preferably 10 to 100 ppm. The sum of Sulphur content and Selenium is acquired with methods known to the skilled artisan, for example as described in WO 2007/014868 and WO 99/19521.

According to the present invention, the High Angle (> 15°) primary Grain Boundary average density is preferably 0.005 to 0.1 µm^-1, more preferably 0.01 to 0.09 µm^-1. The High Angle (> 15°) primary Grain Boundary average density is acquired with methods known to the skilled artisan, for example the Grain Boundary density is measured as primary grain boundary length per unit area and is provided directly by EBSD analysis (OIM Analysis software). The ρHAGB is the average of the values corresponding to misorientations higher than 15° (>15°).

One particularly essential feature of the present invention is that step (D) of the process according to the present invention is conducted at the above defined temperature OTAG2, wherein OTAG2 is calculated according formula (I).

The heating in step (D) of the process according to the present invention is conducted at a heating rate of at least 40 K/s. Preferably, the heating in step (D) of the process according to the present invention is conducted at a heating rate of at least 70 K/s, more preferably at least 100 K/s. This rapid heating can be conducted by any method known to the skilled artisan, for example by induction, by resistive heating, by conductive heating.

The heating in step (D) of the process according to the present invention is preferably conducted at a dew point of 223 to 273 K, particularly preferably 243 to 270 K.

In step (D) of the process according to the present invention the Secondary Recrystallization is performed so that a grain-oriented steel sheet according to the present invention is obtained.

In general, after step (D) of the process according to the present invention, a grain-oriented steel sheet having the advantageous properties as outlined above is obtained.

According to a preferred embodiment of the process according to the present invention, the cold strip that is introduced into step (D) does not comprise any annealing separators, preferably no MgO based coating.

Preferably, further process steps are conducted after step (D).

Preferably, the strip or sheet that is obtained after step (D) of the process according to the present invention is rapidly heated to a temperature of 1423 K or above. This heating step is preferably conducted under a protective gas atmosphere, for example comprising H₂. Particularly preferably, the soaking at a temperature of 1423 K or above is conducted in an atmosphere comprising 5 to 95 vol.-% H₂, balance nitrogen or any inert gas or mix gas with a DP of at least 10 °C. The soaking is preferably conducted to remove disturbing atoms, in particular to remove N and S. In a more preferable practice the soaking temperature above 1523K is chosen.

According to a preferred embodiment of the process according to the present invention, the strip or sheet is heated in step (D) to a temperature of 1423 K or above. More preferably, the strip or sheet is heated in step (D) to a temperature of 1523 K or above.

Further preferred, the steel strip is cooled down afterwards, in particular by methods known to the skilled artisan, for example by natural cooling down to room temperature.

In addition, according to a preferred embodiment of the process according to the present invention, the steel strip is cleaned, and optionally pickled. Methods with which the steel strip is pickled are known to the skilled artisan. Preferably, the steel strip is treated with an aqueous acidic solution. Suitable acids are for example phosphoric acid, sulfuric acid and/or hydrochloric acid. According to the present invention, the grain oriented electrical steel sheets can be prepared in any format, like steel strips that are provided as coils, or cut steel pieces that are provided by cutting these steel pieces from the steel strips. Methods to provide coils or cut steel pieces are known to the skilled artisan.

The present invention provides a process for the preparation of grain-oriented electrical steel sheets comprising a continuous strip annealing treatment for which the temperature is homogeneous and therefore the SRX strip temperature can be optimized and better controlled each portion of the strip. The present invention therefore provides an improved process for the preparation of grain oriented electrical steel which does not comprise the problems of the known processes as mentioned above, in particular SRX shall be optimized. Further, a more efficient way of handling energy during the production should be found.

The present invention further relates to a grain-oriented steel strip prepared by the process according to the present invention. The grain-oriented steel strip prepared by the process according to the present comprises a very advantageous magnetic characteristics, in particular Peak Magnetic Polarization for the peak magnetic field strength of 800 A/m at 50 Hz of 1.85 to 1.98 T, which is essentially obtained due to the specific heat treatment in step (D) of the process.

The grain-oriented steel strip prepared by the process according to the present invention preferably has a thickness of 0.05 to 0.35 mm, more preferably 0.10 to 0.22 mm.

The grain-oriented steel strip prepared by the process according to the present invention preferably has an Average Primary Grain Size of 5 to 25 µm.

The grain-oriented steel strip prepared by the process according to the present invention preferably has a High Angle (> 15°) primary Grain Boundary average density of 0.005 to 0.1 µm^-1.

The grain-oriented steel strip prepared by the process according to the present invention preferably has a Content of Sulphur and/or Selenium of 0.0001 to 0.01 % by weight.

The grain-oriented steel strip prepared by the process according to the present invention preferably has a Nitriding Degree of 0 to 300 ppm.

The grain-oriented steel strip prepared by the process according to the present invention preferably has a Peak Magnetic Polarization for the peak magnetic field strength of 800 A/m at 50 Hz of 1.85 to 1.98 T.

The present invention therefore further relates to a grain-oriented steel strip having a Peak Magnetic Polarization for the peak magnetic field strength of 800 A/m at 50 Hz of 1.85 to 1.98 T. Preferably this grain-oriented steel strip comprises one further characteristic feature like thickness, Average Primary Grain Size, High Angle (> 15°) primary Grain Boundary average density, Content of Sulphur and/or Selenium and/or Nitriding Degree as mentioned above. The present invention also relates to the use of a steel strip according to the present invention in electric transformers, in electric motors or in electric devices, preferably where magnetic flux has to be channeled or contained.

The present invention is described on the basis of the following examples:

A steel with the composition of 3.15% by weight Si, 0.052% by weight C, 0.149% by weight Mn, 0.005% by weight S, 0.207% by weight Cu, 0.030% by weight Al, 0.008% by weight N undergoes a steelmaking and a hot melt casting. The bars are hot rolled into hot band strips which undergo a hot strip annealing and pickling, all processing steps in accordance with DE 19745455 C1 and EP 1 752 549 B1.

The strip is cold rolled in a first cold rolling step down to an intermediate thickness of 0.50 mm and then decarburized at an Intermediate Annealing stage (840 °C in wet atmosphere with Dew Point of 58 °C) and pickled with Sulfuric acid (68°C for 30 s). The second cold rolling is performed to reach a final thickness of 0.18 mm. Afterwards the final strip undergoes a fast annealing nitriding treatment leading to a Nitriding Degree, delta N of 150 ppm, measured with a Nitrogen Elemental Analyzer of A36 LECO Corporation. The primary recrystallized material is characterized by an average grain size of 19 µm, which is measured with a Grain size measured by EBSD analysis (OIM Analysis software) and being the average grain size, and an average High Angle primary Grain Boundary density of 0.071 µm^-1, which is measured with a Grain Boundary density is measured as primary grain boundary length per unit area and is provided directly by EBSD analysis (OIM Analysis software). The pHAGB is the average of the values corresponding to misorientations higher than 15° (>15°).

The final secondary recrystallization treatment is done according to following conditions; a single sample is placed inside an oven and undergoes an ultra-rapid heating rate of 250 K/s under dry N₂ protective gas atmosphere (Dew Point 243 K) up to a 1350 K soaking temperature under a dry mixture of H₂₂, N₂ and Ar as protective gas atmosphere to perform the Secondary Recrystallization.

Afterwards the strip is rapidly heated up to 1500 K temperature to perform a purification soaking under a slightly wet (DP is 288 K) H₂ protective gas atmosphere, in order to remove N and S. Finally the strip sample is cooled down, cleaned and slightly pickled before magnetic property measurements. Finally the sample is pickled with hydrochloric acid 37% at 60°C for 15s to observe the grain macrostructure.

The outputs of this experimentation were a completed secondary recrystallized macrostructure having an excellent magnetic polarization J800 of 1.92 T, measured according to IEC 60404-2

A steel with the composition of 3.10% by weight Si, 0.047% by weight C, 0.155% by weight Mn, 0.008% by weight S, 0.199% by weight Cu, 0.030% by weight Al, 0.009% by weight N undergoes a steelmaking and a hot melt casting. The bars are hot rolled into hot band strips which undergo a hot strip annealing and pickling, all processing steps in accordance with DE 19745455 C1 and EP 1 752 549 B1.

The strip is cold rolled in a first cold rolling step down to an intermediate thickness of 0.36 mm and then decarburized at Intermediate Annealing stage (840 °C in wet atmosphere with Dew Point: 58 °C) and pickled with Sulfuric acid (68°C for 30 s). The second cold rolling is performed to reach a final thickness of 0.18 mm. Afterwards the final strip undergoes a fast annealing nitriding treatment leading to a Nitriding Degree of delta N 152 ppm. The primary recrystallized material is characterized by an average grain size of 14 µm and an average High Angle primary Grain Boundary density of 0.010 µm^-1.

The final secondary recrystallization treatment is done according to following conditions; a single sample is placed inside an oven and undergoes a ultra-rapid heating rate of 15 K/s under dry N₂ protective gas atmosphere (DP 243 K) up to a 1250 K soaking temperature under a dry mixture of H₂, N₂ and Ar as protective gas atmosphere to perform the Secondary Recrystallization.

Afterwards the strip is rapidly heated up to a 1500 K temperature to perform a purification soaking under a slightly wet 288 K H₂ protective gas atmosphere, in order to remove N and S. Finally the strip sample is cooled down, cleaned and slightly pickled with Sulfuric acid (68 °C for 15 s) before magnetic property measurements. Finally the sample is pickled with hydrochloric acid 37% at 60 °C for 15s to observe the grain macrostructure.

The outputs of this experimentation were a not completed secondary recrystallized macrostructure having a poor magnetic polarization J800 of 1.45 T measured according to IEC 60404-2.

Further experiments according to the present invention have been conducted according to examples 1 and 2. The conditions and results of these experiments are shown in the following. No. Heating rate in Secondary Recrystallization [K/s] Dew Point during heating rate [K] Soaking Temperature for SRX [K] Average Primary Grain Size [µm] High Angle (> 15°) Grain Boundary average density [µm^-1] Content of Sulphur and/or Selenium [ppm] Nitriding Degree [ppm] Peak magnetic polarization for the peak magnetic field strength of 800 A/m at 50 Hz [T] Secondary Recrystallization 1 75 243 1350 17 0.067 45 112 1.90 completed 2 75 253 1320 17 0.080 50 60 1.88 completed 3 75 263 1290 20 0.087 40 57 1.87 completed 4 125 243 1350 14 0.064 45 115 1.93 completed 5 125 253 1320 18 0.075 50 62 1.89 completed 6 125 263 1290 20 0.086 70 70 1.88 completed 7 250 243 1350 19 0.071 50 150 1.92 completed 8 250 253 1320 17 0.085 60 80 1.91 completed 9 250 263 1290 19 0.086 70 72 1.89 completed 10 500 243 1350 19 0.077 45 135 1.92 completed 11 500 253 1320 16 0.090 25 125 1.91 completed 12 500 263 1290 20 0.078 25 27 1.92 completed 13 50 263 1350 18 0.045 50 100 1.88 completed 14 150 263 1350 18 0.055 50 85 1.89 completed 15 300 253 141b 9 0.060 30 70 1.92 completed 16 500 263 1415 6 0.020 20 21 1.90 completed 17 600 263 1415 13 0.029 30 20 1.91 completed 18 700 243 1415 17 0.067 40 105 1.92 completed C19 15 243 1250 18 0.070 25 99 1.63 not completed C20 15 243 1250 14 0.010 80 152 1.45 not completed C21 20 273 1250 15 0.088 90 63 1.66 not completed C22 75 288 1250 22 0.044 30 110 1.49 not completed C23 250 253 1250 4 0.001 25 265 1.45 not completed C24 350 243 1250 4 0.002 25 170 1.47 not completed C25 500 273 1250 4 0.003 50 9 1.46 not completed C26 800 243 1250 15 0.005 60 132 1.46 not completed C: comparative example No. Peak magnetic polarization for the peak magnetic field strength of 800 A/m at 50 Hz Soaking Temperature for SRX calculated OTAG2 [T] [K] OTAG2 bottom limit [K] OTAG2 upper limit [K] 1 1.90 1350 1320 1420 2 1.88 1320 1288 1420 3 1.87 1290 1241 1420 4 1.93 1350 1322 1420 5 1.89 1320 1300 1420 6 1.88 1290 1266 1420 7 1.92 1350 1324 1420 8 1.91 1320 1307 1420 9 1.89 1290 1288 1420 10 1.92 1350 1323 1420 11 1.91 1320 1318 1420 12 1.92 1290 1288 1420 13 1.88 1350 1337 1420 14 1.89 1350 1333 1420 15 1.92 1415 1377 1420 16 1.90 1415 1410 1420 17 1.91 1415 1389 1420 18 1.92 1415 1345 1420 C19 1.63 1250 1264 1420 C20 1.45 1250 1405 1420 C21 1.66 1250 1255 1420 C22 1.49 1250 1318 1420 C23 1.45 1250 1420 1420 C24 1.47 1250 1420 1420 C25 1.46 1250 1419 1420 C26 1.46 1250 1415 1420 C: comparative example

OTAG2 has been calculated according to the following formula (I) $$\mathrm{1420}\mathrm{K}-\mathrm{DP}\times \mathrm{PGS}\times \mathrm{\rho HAGB}/\log \left(\left(\mathrm{S}+\mathrm{\Delta N}\right)\times \mathrm{HRSRX}/\mathrm{20}\right)<\mathrm{OTAG}\mathrm{2}<\mathrm{1420}\mathrm{K}$$ wherein OTAG2, HRSRX, PGS, ΔN, DP, S and pHAGB have the following meanings:

OTAG2

Optimum Temperature of Abnormal Grain Growth in K,

HRSRX

Heating Rate to Secondary Recrystallization Treatment in K/s,

PGS

Average Primary Grain Size in µm,

ΔN

Nitriding Degree in ppm, calculated by Nitrogen Degree in ppm before SRX annealing (D) minus Nitrogen Degree in ppm before primary recrystallization annealing (C),

DP

Atmosphere Dew Point during heating rate in K,

S

sum of Sulphur content and Selenium content in ppm,

pHAGB

High Angle (> 15°) primary Grain Boundary average density in µm^-1.

The grain-oriented electrical steel sheet according to the present invention shows a very high Peak Magnetic Polarization and is therefore very useful in electric transformers, in electric motors or in electric devices, preferably where magnetic flux has to be channeled or contained.