EP0601549A1 - Tôle d'acier électrique - Google Patents

Tôle d'acier électrique Download PDF

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Publication number
EP0601549A1
EP0601549A1 EP93119720A EP93119720A EP0601549A1 EP 0601549 A1 EP0601549 A1 EP 0601549A1 EP 93119720 A EP93119720 A EP 93119720A EP 93119720 A EP93119720 A EP 93119720A EP 0601549 A1 EP0601549 A1 EP 0601549A1
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steel sheet
grain boundaries
electrical steel
content
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EP0601549B1 (fr
Inventor
Yasushi C/O Intellectual Prop. Dept. Tanaka
Tatsuhiko C/O Intellectual Prop. Dept. Hiratani
Masahiro C/O Intellectual Prop. Dept. Abe
Katsuji C/O Intellectual Prop. Dept. Kasai
Kazuhisa C/O Intellectual Prop. Dept. Okada
Masaru C/O Intellectual Prop. Dept. Ishikawa
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JFE Engineering Corp
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NKK Corp
Nippon Kokan Ltd
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Priority claimed from JP4351859A external-priority patent/JP2956399B2/ja
Priority claimed from JP5028562A external-priority patent/JP2956406B2/ja
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Publication of EP0601549A1 publication Critical patent/EP0601549A1/fr
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1272—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/773—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material under reduced pressure or vacuum
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • C21D8/1227—Warm rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1255—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding

Definitions

  • the present invention relates to a high silicon electrical steel sheet used for a core material of transformers and electric motors.
  • An electrical steel sheet is widely used as a core material of electric motors and transformers.
  • the electrical steel sheet generally contains silicon to control a texture and to improve specific resistance.
  • An iron alloy containing 6.5 wt.% silicon exhibits best soil magnetic property owing to their magnetostriction substantially near to zero.
  • increase of silicon content makes steel brittle, and high silicon steel containing silicon at 4 wt.% or more can not be formed to a thin steel sheet using an ordinary rolling method.
  • several methods to obtain a high silicon thin steel sheet have been proposed.
  • One of them is direct production by rapid solidification which produces the high silicon thin steel sheet directly from melt by casting, which method, for example, is disclosed in Japanese Examined Patent Publication No. 60-32705.
  • Another one is application of a special rolling method, which method, for example, is disclosed in Japanese Examined Patent Publication No. 3-80846 and a further one is a siliconizing method where silicon is enriched into a low silicon steel sheet prepared by rolling, which method, for example, is disclosed in Japanese Examined Patent Publication 2-60041.
  • the siliconizing method has already been brought into commercial use.
  • a high silicon steel sheet prepared by either one of the methods described above is necessary to be processed by punching, shearing, and bending before applying to the electric motors and the transformers.
  • the high silicon steel sheet has, however, a problem of brittleness which induces cracks and chips at punched or sheared corners and tends to generate breaks during a bending process.
  • Japanese Examined Patent Publication No. 61-15136 discloses a method to obtain a high silicon steel sheet having superior workability and magnetic characteristic by controlling a grain size to a range of from 1 to 100 ⁇ m and by controlling the crystal grains to have columnar crystals grown vertically to a thin sheet surface while substantially eliminating ordered lattice.
  • Japanese Unexamined Patent Publication No. 62-270723 discloses a method to obtain a high silicon steel sheet having substantially high workability by forming a steel having as-rolled texture into a product shape followed by annealing.
  • Japanese Unexamined Patent Publication No. 4-165050 discloses a method to obtain a high silicon grain-oriented steel sheet having high workability by adding Mn to suppress bad influence of solid solution of sulfur and by increasing grain orientation.
  • the method of Japanese Examined Patent Publication No. 61-15136 does not give its target effect when the grain diameter increases to 100 ⁇ m or more, and, for a high silicon steel, the method needs to employ a quenching step such as water-quenching from a high temperature of 900°C or more to substantially eliminate a ordered grain phase. Consequently, the method faces a difficulty in practical application.
  • the method of Japanese Examined Patent Publication No. 62-270723 employs a working of steel having rolled texture so that the method needs high temperature annealing after the working.
  • the method has a disadvantage of adding an extra step to the manufacturing processes of the transformers and the electric motors.
  • Japanese Unexamined Patent Publication No. 4-1605050 needs to use highly grain oriented steel. Obtaining the high grain orientation is difficult owing to poor stability of secondary re-crystallization using inhibitor. In addition, this method has a disadvantage that it can not be applied to a non-oriented silicon steel sheet.
  • An object of the invention is to provide an electrical steel sheet having high workability.
  • the present invention provides an electrical steel sheet containing Si of 4 to 10 wt.%, which comprises: said electrical steel sheet containing crystal grains and grain boundaries, said grain boundaries having an oxygen content of 30 atomic % or less.
  • the electrical steel sheet further preferably consists essentially of: 0.01 wt.% or less C, 4 to 10 wt.% Si, 0.5 wt.% or less Mn, 0.01 wt.% or less P, 0.01 wt.% or less S, 0.2 wt.% or less Sol. (Aluminium in the state of solid solution), Al./0.01 wt.% or less N, 0.02 wt.% or less O, and the balance being Fe and inevitable impurities.
  • the present invention provides an electrical steel sheet containing (Si + Al) of 4 to 10 wt.%, which comprises: said electrical steel sheet containing crystal grains and grain boundaries, said grain boundaries having the oxygen content of 30 atomic % or less.
  • the electrical steel sheet further preferably consists essentially of: 0.01 wt.% or less C, 4 to 10 wt.% (Si + Al), 0.5 wt.% or less Mn, 0.01 wt.% or less P, 0.01 wt.% or less S, 0.01 wt.% or less N, 0.02 wt.% or less O, and the balance being Fe and inevitable impurities.
  • the present invention provides an electrical steel sheet containing Si of 4 to 10 wt.%, which comprises: said electrical steel sheet containing crystal grains and grain boundaries, said grain boundaries having the oxygen content of 30 atomic % or less and a sulfur content of 0.2 atomic % or less.
  • the electrical steel sheet further preferably consists essentially of: 0.01 wt.% or less C, 4 to 10 wt.% Si, 0.5 wt.% or less Mn, 0.01 wt.% or less P, 0.01 wt.% or less S, 0.2 wt.% or less Sol. Al, 0.01 wt.% or less N, 0.02 wt.% or less O, and the balance being Fe and inevitable impurities.
  • the present invention provides an electrical steel sheet containing (Si + Al) of 4 to 10 wt.%, which comprises: said electrical steel sheet containing crystal grains and grain boundaries, said grain boundaries having the oxygen content of 30 atomic % or less and the sulfur content of 0.2 atomic % or less.
  • the electrical steel sheet further preferably consists essentially of: 0.01 wt.% or less C, 4 to 10 wt.% (Si + Al), 0.5 wt.% or less Mn, 0.01 wt.% or less P, 0.01 wt.% or less S, 0.01 wt.% or less N, 0.02 wt.% or less O, and the balance being Fe and inevitable impurities.
  • a mother phase of a high silicon steel sheet is brittle in nature, the sheet has been considered substantially unable to improve the workability.
  • the inventors have carried a series of experiment aiming at improvement of the workability of the high silicon steel sheet focusing on the workability under various levels of dew points and oxygen concentrations in an atmosphere of final heat treatment, and found that there exist a steel sheet which shows relatively high workability among others while containing the same percentage of silicon.
  • Fig. 1 shows a test result of the workability of the steel sheet. Degree of vacuum was varied in the test to change the dew point and the oxygen concentration in an annealing atmosphere.
  • a horizontal axis represents the degree of vacuum
  • a vertical axis represents a bend amount of a specimen in a three points bending test (the test to determine the maximum stroke before breaking the specimen under a condition of pressing down shown in Fig. 5) as an index of the workability.
  • the annealing was carried out at 1,200°C for 15min. The test result showed that the higher the degree of vacuum is, the more the workability improved.
  • Carbon is a harmful element for soil magnetic property, and when C content exceeds 0.01 wt.%, the soil magnetic property degrades with time, which phenomenon is called "age degrading". To avoid such a disadvantage, the C content of 0.01 wt.% or less is preferable.
  • Silicon content of approximately 6.5% makes the magnetostriction zero and shows the best soil magnetic property.
  • Si content is less than 4 wt.%, the silicon steel sheet does not show a wanted magnetic property, and the workability of the steel sheet raises no specific problem.
  • Si content exceeds 10 wt.%, saturation flux density significantly decreases. Therefore, the Si content is specified as in a range of from 4 to 10 wt.%.
  • a part of Si is able to be substituted with Al.
  • total quantity of Si + Al is necessary to be specified.
  • the total quantity of Si + Al is less than 4 wt.%, the magnetic characteristics being aimed by the present invention can not be attained, and the workability of the steel sheet raises no specific problem.
  • the Si content exceeds 10 wt.%, the saturation flux density significantly decreases. Consequently, when a part of Si is substituted by Al, the total quantity of Si + Al is preferably specified as in a range of from 4 to 10 wt.%.
  • Manganese combines with S to form MnS to improve hot workability in a slab stage.
  • Mn content exceeds 0.5 wt.%, however, reduction of the saturation flux density becomes significant, which is not preferable. Accordingly, the Mn content of 0.5 wt.% or less is preferable.
  • Phosphorus is an element of degrading the soil magnetic property, and the content is preferred to decrease as far as possible. Since the P content of 0.01 wt.% or less raises substantially no bad influence and is preferred from economy, it is preferable that the P content is specified as 0.01 wt.% or less.
  • Sulfur is an element to increase brittleness during a hot rolling stage and to degrade the soft magnetic property. Consequently, the content is preferred to decrease as far as possible. Since the S content of 0.01 wt.% or less raises substantially no bad influence and is preferred from the economy, the S content of 0.01 wt.% or less is desirable.
  • Aluminum has an ability to clean steel by deoxidation and, from a viewpoint of the magnetic property, has a function to increase electric resistance.
  • the Sol. Al content is preferably specified as 0.2 wt.% or less.
  • a total Si + Al content is specified as in a range of from 4 to 10 wt.%, as described above.
  • Nitrogen is an element of degrading the soft magnetic property and also of inducing an age change of the magnetic property, so the content is preferred to decrease as far as possible. Since the N content of 0.01 wt.% or less raises substantially no bad influence and is preferred from the economy, the N content of 0.01 wt.% or less is preferable.
  • Oxygen is an element of degrading the soft magnetic property, and the content is preferred to decrease as far as possible.
  • the most important factor in the present invention is the oxygen content in the grain boundaries, and the O content is total quantity of O in both the grain boundaries and inside of grains.
  • the present invention provides superior workability by controlling the content of oxygen in the grain boundaries which is unavoidably existing in the steel sheet, which is described later.
  • the O content in the steel sheet exceeds 0.02 wt.%, oxygen exists in both the grain boundaries and the inside of grains under all heat treatment conditions, and the state makes difficult to decrease the Oxygen content in the grain boundaries to 30 at.% or less.
  • the O content is specified as 0.02 wt.% or less.
  • a lower limit of the O content is not specifically defined. Simple reduction of the O content does not induce a decrease of the O concentration in the grain boundaries. However, excess reduction of O increases production costs. Consequently, from a economical reason, it is not preferable to reduce the O content to below 0.0005 wt.%.
  • impurities of steel may include Cr, Ni, Cu, Sn, and Mo. Presence of each of these elements at approximately 0.03 wt.% does not affect the effect of the present invention.
  • the O content in the grain boundaries (the O content in elements segregated to the grain boundaries) of the steel of the present invention is required to be 30 at.% (atomic percent) or less. This is the most important condition of the present invention.
  • the O content at the grain boundaries means the oxygen content (at.%) in the elements segregated to the grain boundaries.
  • Auger electron spectroscopy is employed to determine the oxygen content. According to the spectroscopy, a specimen is broken in a vacuum chamber which is held at 1 ⁇ (1/109) Torr or less, and the Auger electron spectrometry is applied while observing an intergranular fractured surface where is not polluted by atmospheric air. This procedure allows an elemental analysis on the clean intergranular fractured surface.
  • An energy position to measure the Auger electron intensity is defined for each element.
  • Fe uses a peak on a highest energy side among three LMM transitions
  • O uses a KLL transition
  • C uses the KLL transition
  • S uses a LVV transition.
  • the relative sensitivity was already known for each element transition, and these values are described in a literature cited above. According to Phai's unit, a value is 0.220 for Fe, 0.140 for C, 0.400 for O, and 0.750 for S.
  • the Auger electron spectroscopy has been widely used to determine an element quantitative value. Accordingly, the present invention also adopted this method to determine the elements at the grain boundaries.
  • the inventors employed this method to determine the grain boundaries on each of the materials of superior workability and of inferior workability, and carried out the elemental analysis at the grain boundaries, and found that the O content at the grain boundaries has an extremely strong relation with a degree of easiness of workability.
  • Fig. 2 shows a relation between elongation and the O content in the grain boundaries determined by the Auger electron spectroscopy using a high silicon steel sheet having chemical composition listed in Table 1 and having plate thickness of 0.1 mm.
  • a steel sheet containing less O in the grain boundaries shows better elongation Among steel sheets tested, the ones showing 3% or higher elongation gave plastic deformation.
  • an observation of scanning electron microscope on a fractured surface revealed that the steel sheet having superior elongation gave rather a cleavage fracture than a grain boundary fracture and that the steel sheet having inferior elongation showed a tendency toward the grain boundary fracture.
  • this type of high silicon steel sheet was accepted to induce no plastic deformation.
  • the present invention specifies the O content as 30 at.% or less. From Fig. 2, the O content of 15 at.% or less in the grain boundaries provides better workability.
  • the carbon in the grain boundaries has been found to clearly play an important role on workability.
  • the C content in grain boundaries the C content in the elements segregated to the grain boundaries
  • the elongation is further improved and workabitity was improved.
  • the Carbon in the grain boundaries are considered to have a suppression function against grain boundary cracks, though a detailed mechanism is not known yet.
  • Fig. 3 shows a relation between a grain boundary intensity parameter and a three points bending characteristic.
  • the workability shown in the three points bending characteristic has an extremely strong relation with the grain boundary intensity parameter which was described above.
  • the bend amount in three point bending test is 5 mm or more
  • the workability is judged improved compared with prior art materials, so values of (C/Fe)/(O/Fe) (grain boundary intensity parameter) is 0.5 or more suggests the improved workability.
  • the bend amount in three point bending test is 10 mm or more, the workability is concluded to be significantly improved. Therefore, the grain boundary intensity parameter is preferred to specify as 1.0 or more.
  • the C content in the grain boundaries when the O content in the grain boundaries exceeds 30 at.%, there appears no effect of improvement of workability, and when the O content in the grain boundaries is below 30 at.%, if the C content in the grain boundaries is 0.5 at.% or more, the grain boundary intensity increases and the workability is improved. Consequently, the C content in the grain boundaries is preferred to specify as 0.5 at.% or more. For further improvement of workability, the C content in grain boundaries is preferably specified as 0.8 at.% or more.
  • the high silicon steel sheet having the chemical composition listed in Table 1
  • the high silicon steel sheet having the O content in the grain boundaries of approximately 5 at.% and the C content in the grain boundaries of approximately 1 at.% were tested to determine the relation between the average grain diameter viewed from the sheet surface and the three points bending characteristic under various grain diameters.
  • the result is shown in Fig. 4. According to the figure, the workability is improved by specifying the average grain diameter as 2.0 mm or less.
  • the high silicon steel sheet employed in the experiments described above has extremely good crystal grain growth to form coarse grains by heat treatment, and tend to form a bamboo structure where the crystal grains penetrate in the sheet thickness direction. Nevertheless, as described before, the grain diameter of the steel sheet is preferably at 2.0 mm or less from a viewpoint of the workability, and the steel sheet needs to select a controlled heat treatment condition not to yield excessively coarse grains.
  • the present inventors found that the growth of crystal grains substantially stops at the diameter of approximately 3 to 4 times of the steel sheet thickness. Consequently, to hold the grain diameter at 2.0 mm or less, the sheet thickness may be selected as 0.5 mm or less. In this case, there is no need for care of the heat treatment condition. From these reasons, the preferable thickness of the steel sheet is 0.5 mm or less.
  • the effect of the present invention is obtained independent of the grain orientation distribution in the silicon steel sheet. Therefore, the present invention does not specify either an oriented silicon steel sheet or a non-oriented silicon steel sheet.
  • An ordinary electrical steel sheet is coated by film for insulation, and the present invention is independent of presence of the coating film.
  • the present invention does not specify a method of preparing a thin sheet, and the present invention is applicable to the high silicon steel sheet manufactured by the special rolling method, the siliconizing method, which were described before, and other adequate methods.
  • Fig. 6 shows an effect of the O content in the grain boundaries on the bend amount in the three point bending test. The figure shows that decrease of the O content in the grain boundaries clearly increases the bend amount, which suggests that the lower O content in the grain boundaries gives better workability.
  • the heat treatment was carried out under several atmospheric conditions. Those prepared specimens were subjected to the three points bending test.
  • the samples for the Auger electron spectroscopy were prepared from residuals of the specimens for the three points bending test. These samples were fractured under a vacuum condition in the Auger electron spectrometer to determine the composition in terms of O and C in the grain boundaries. A relation among the O content and the C content in the grain boundaries and the three points bending characteristic were studied. For specimens of the O content above 30 at.% in the grain boundaries, there was no relation among the O content and the C content in the grain boundaries and the bend amount. For the specimens of the O content at 30 at.% or less, however, there was a clear relation among them.
  • Fig. 7 shows the relation between the C content in the grain boundaries and the three points bending characteristic for the specimens (average grain diameter: 0.19 mm) having the O content in the grain boundaries at approximately 10 at.%. According to the figure, the steel containing C in the grain boundaries to some extent clearly improved the workability.
  • Example 1 and Example 2 Specimens tested in Example 1 and Example 2 were subjected to a shearing test using a shearing tester having clearance of 3 ⁇ m. A sheared surface was observed under an optical microscope ( ⁇ 200) to count the number of defects such as cracks per 10 cm of shear length. The result is shown in Fig. 8 relating to the O content in the grain boundaries. The figure represents the same tendency with the result of three points bending test, and it clearly indicates the effect of a limitation of the O content in the grain boundaries.
  • the C content in the grain boundaries was in a range of from 0.2 to 0.8 at.%, and the average grain diameter was in a range of from 1 to 1.4 mm.
  • the result is shown in Fig. 9. The figure shows that a steel sheet having low O content in the grain boundaries gave larger elongation.
  • Table 4 shows the average grain diameter and the three points bending test result for each specimen.
  • the table shows that larger average grain diameter totally degrades a bending characteristic.
  • the bending characteristic significantly degrades.
  • the bending characteristic is inferior even the average grain diameter is 2.0 mm or less.
  • a silicon steel sheet (thickness: 0.3 mm) having a chemical composition listed in Table 5 was prepared.
  • the sheet was subjected to siliconization - diffusion treatment (Si diffusion and penetration treatment) to manufacture a 6.5% silicon steel sheet.
  • the siliconization was carried by employing two different mixed gases as a carrier gas: one was mixed with high purity nitrogen gas (dew point: -70°C) and the other was mixed with ordinary nitrogen gas (dew point: -30°C). Obtained specimens were subjected to the three points bending test, and residual specimens were analyzed by the Auger electron spectrometer to determine the O content in the grain boundaries.
  • Fig. 11 shows a relation between the three points bending characteristic (the stroke of pressing-in of the specimen in the three points bending tester described before) and the S content detected at the grain boundaries using the Auger electron spectrometer.
  • the specimen used here had composition of 6.49 wt.% Si, 0.005 wt.% Mn, 0.0015 wt.% S, and 0.0022 wt.% O, having a thickness of 0.35 mm, and was heat-treated in N2 atmosphere containing 0.1 vol.% of H2S.
  • the specimens after the heat treatment gave nearly same quantity of total S within an analytical error.
  • the O content in the grain boundaries determined by the Auger electron spectrometer gave in a range of from 3 to 5 at.% for all specimens tested. According to Fig. 11, the workability has a strong relation with the S content in the grain boundaries, which suggests that the S in the grain boundaries degrades the workability.
  • the control of the grain size is easily done by changing the annealing temperature.
  • the tests described above showed, however, that the change of annealing temperature largely changes the workability.
  • the inventors found that the workability of the high silicon steel sheet which had long been considered to be inferior in nature for working has an extremely strong correlation to the characteristics of the grain boundaries and that control of the characteristics provides the high silicon steel sheet having excellent workability.
  • the high silicon steel sheet having thickness of 0.1 mm and having chemical composition listed in Table 6, and having almost the same O content in the grain boundaries determined by the Auger electron spectrometer were employed to determine a relation between the elongation and the S content in the grain boundaries measured by the Auger electron spectrometer.
  • the result is shown in Fig. 12.
  • the figure shows that a specimen having less S content in the grain boundaries gives high elongation.
  • specimens which gave the elongation of 3% or more yielded plastic deformation.
  • Observation of the fractured surface by the scanning electron microscope revealed that the specimens giving high elongation gave rather cleavage fracture than grain boundary fracture and that the steel sheet having inferior elongation showed the tendency toward the grain boundary fracture.
  • the present invention needs to specify not only the S content in the grain boundaries as described above but also the O content in the grain boundaries (the O content in the elements segregated to the grain boundaries) to 30 at.% (atomic percent) or less.
  • an effect of a reduction of the S content in the grain boundaries is acquired only when the O content in the grain boundaries is sufficiently low.
  • the O content in the grain boundaries is necessary to decrease as low as 30 at.% or less.
  • Fig. 13 shows a relation between the three points bending characteristic (the stroke of pressing-in of the specimen in the three points bending tester described before) and the S content in the grain boundaries.
  • a specimen used here had composition of 6.66 wt.% Si, 0.001 wt.% S, 0.001 wt.% Sol.
  • the present invention specifies the O content in the grain boundaries as 30 at.% or less, most preferably as 15 at.% or less.
  • the grain diameter was found to affect the workability. It was found that when the average grain diameter viewed from the sheet surface was 2.0 mm or less, the workability was further improved. The reason for the effect is speculated that the intensity within the grains relatively decreased corresponding to the increase of intensity of the grain boundaries owing to the effect of S at the grain boundaries, which enhances the cracks across the grains, so an excessive grain diameter degrades the workability.
  • the high silicon steel sheets having the O content in the grain boundaries of approximately 5 at.%, the C content in the grain boundaries of approximately 1 at.%, and the S content in the grain boundaries of approximately 0.05 at.% were tested to determine a relation between the average grain diameter viewed from the sheet surface and the three points bending characteristic under various grain diameters.
  • the result is shown in Fig. 14. According to the figure, the workability is improved by specifying the average grain diameter as 2.0 mm or less.
  • the high silicon steel sheets employed in experiments described above have extremely good crystal grain growth to form coarse grains, and tend to form the bamboo structure where the crystal grains penetrate in the sheet thickness direction. Nevertheless, as described before, the grain diameter of the steel is preferably at 2.0 mm or less from the viewpoint of workability, and the steel needs to select the controlled heat treatment condition not to yield excessively coarse grains.
  • the crystal structure of the high silicon steel sheet forms the bamboo structure
  • the present inventors found that the growth of crystal grains substantially stops at the diameter of approximately 3 to 4 times the steel sheet thickness. Consequently, to hold the grain diameter at 2.0 mm or less, the sheet thickness may be selected as 0.5 mm or less. In this case, there is no need for the care of heat treatment condition. From these reasons, the preferable thickness of the steel sheet is 0.5 mm or less.
  • the effect of the present invention is obtained independent of the grain orientation distribution in the silicon steel sheet. Therefore, the present invention does not specify either a oriented silicon steel sheet or a non-oriented silicon steel sheet.
  • An ordinary electric steel sheet is coated by film for insulation, and the present invention is independent of presence of the coating film.
  • the present invention does not specify the method of preparing a thin sheet, and the present invention is applicable to the high silicon steel sheet manufactured by the special rolling method, the siliconizing method, which were described before, and other appropriate methods.
  • a high silicon steel sheet (thickness: 0.1 mm) having composition listed in Table 7 was subjected to the heat treatment (final annealing) at 1,200°C for 15 min. in different reduced pressures ranging from 5 to 1 ⁇ (1/105) Torr.
  • An ambient temperature in a laboratory was 27°C and humidity was 80%. Obtained specimens were tested by the three points bending machine to determine the maximum pressing-in stroke before fracturing. The remainder of each specimen was placed in the Auger electron spectrometer to fracture in a vacuum of 8 ⁇ (1/1010) Torr. A fractured surface of each specimen was observed, and composition at the grain boundaries was analyzed.
  • High silicon steel sheets having a composition listed in Table 8 and having a different thickness were subjected to final annealing at various annealing temperatures ranging from 800 to 1,300°C for 15 min. in reduced pressure of 1 ⁇ (1/104) Torr to prepare specimens having different sheet thicknesses and different average grain diameters. Obtained specimens were tested by the three points bending machine. The remainder of each specimen was placed in the Auger electron spectrometer to determine the O content, the C content, and the S content in the grain boundaries.
  • the Auger electron spectroscopy showed that all the specimens gave the O content in the grain boundaries of 8 ⁇ 2 at.%, the C content in the grain boundaries in a range of from 0.8 to 2 at.%, and the S content in the grain boundaries in a range of from 0.05 to 0.10 at.%.
  • Table 4 shows the average grain diameter and the three points bending test result for each specimen. The table shows that the average grain diameter above 2.0 mm significantly degrades the bending characteristic. For the specimen which thickness exceeds 0.5 mm, the bending characteristic is inferior even the average grain diameter is 2.0 mm or less.
  • a silicon steel sheet (thickness: 0.3 mm) having a chemical composition listed in Table 9 was prepared.
  • the sheet was subjected to the siliconization - diffusion treatment (Si diffusion and penetration treatment) at 1,200°C.
  • the siliconization was carried by employing two different mixed gases as a carrier gas: one was SiCl4 gas mixed with high purity nitrogen gas (dew point: -70°C) and the other was SiCl4 gas mixed with ordinary nitrogen gas (dew point: -30°C).
  • Obtained specimens were subjected to the three points bending test, and residual specimens were analyzed by the Auger electron spectrometer to determine the O content, the C content, and the S content in the grain boundaries.
  • Fig. 16 The figure shows that the limitation of the S content in the grain boundaries is effective for the improvement of workability even for the high silicon steel sheet obtained by the Si diffusion-penetration process.
  • Steel sheet having a thickness of 0.35 mm and having a composition listed in Table 10 was prepared by rolling method, and the sheet was subjected to the heat treatment at 1,200°C for 15 min. under several kinds of nitrogen atmosphere having dew points in a range of from -10 to -70°C and the H2S content in a range of from 0 to 0.1 vol.%.
  • These prepared specimens were tested by the three points bending machine, and the remainder of these specimens were analyzed by the Auger electron spectrometer to measure the O content and the S content in the grain boundaries to determine the effect of the O content and the S content in the grain boundaries on the bend amount of the three point bending test.
  • the result is summarized in Fig. 13.
  • the figure shows that the O content in the grain boundaries of 30 at.% or less gives a relation between the S content in the grain boundaries and the bend amount and that the O content in the grain boundaries of above 30 at.% gives very little change in the three points bending characteristic even when the S content in the grain boundaries decreases to 0.2 at.% or less.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP93119720A 1992-12-08 1993-12-07 TÔle d'acier électrique Expired - Lifetime EP0601549B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP4351859A JP2956399B2 (ja) 1992-12-08 1992-12-08 加工性の優れた高珪素電磁鋼板
JP351859/92 1992-12-08
JP28562/93 1993-01-25
JP5028562A JP2956406B2 (ja) 1993-01-25 1993-01-25 加工性の優れた高珪素電磁鋼板

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EP0601549A1 true EP0601549A1 (fr) 1994-06-15
EP0601549B1 EP0601549B1 (fr) 1997-07-16

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10760143B2 (en) 2015-09-17 2020-09-01 Jfe Steel Corporation High-silicon steel sheet and method of manufacturing the same

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
TW437010B (en) 1998-09-08 2001-05-28 Siemens Ag A layer-arrangement with a material-layer and a diffusion-barrier against diffusable material-components
CN1252304C (zh) * 2003-11-27 2006-04-19 林栋樑 高硅钢及其制备方法
KR100721817B1 (ko) * 2005-12-14 2007-05-28 주식회사 포스코 자성이 우수한 무방향성 전기강판 및 그 제조방법
JP6404356B2 (ja) 2013-12-24 2018-10-10 ポスコＰｏｓｃｏ 軟質高珪素鋼板及びその製造方法

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JPS5822357A (ja) * 1981-07-31 1983-02-09 Matsushita Electric Ind Co Ltd ｛１００｝＜０１１＞集合組織を有する高珪素鋼薄帯とその製造方法
JPS6033860A (ja) * 1983-08-05 1985-02-21 Matsushita Electric Ind Co Ltd 方向性珪素鉄薄帯の製造方法
EP0254932A2 (fr) * 1986-08-01 1988-02-03 AlliedSignal Inc. Procédé de traitement thermique de rubans en alliage Fe-6,5% Si trempé rapidement
JPH02267246A (ja) * 1989-04-05 1990-11-01 Nkk Corp 優れた鉄損特性を有する高珪素鋼板およびその製造方法
JPH03207815A (ja) * 1990-01-04 1991-09-11 Nippon Steel Corp 冷間加工性および磁気特性の良好な高珪素軟磁性鋼板の製造方法
EP0526834A1 (fr) * 1991-07-29 1993-02-10 Nkk Corporation Procédé pour la fabrication de bandes d'acier au silicium ayant une granulation fine disposée en orientation de GOSS

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JPS5822357A (ja) * 1981-07-31 1983-02-09 Matsushita Electric Ind Co Ltd ｛１００｝＜０１１＞集合組織を有する高珪素鋼薄帯とその製造方法
JPS6033860A (ja) * 1983-08-05 1985-02-21 Matsushita Electric Ind Co Ltd 方向性珪素鉄薄帯の製造方法
EP0254932A2 (fr) * 1986-08-01 1988-02-03 AlliedSignal Inc. Procédé de traitement thermique de rubans en alliage Fe-6,5% Si trempé rapidement
JPH02267246A (ja) * 1989-04-05 1990-11-01 Nkk Corp 優れた鉄損特性を有する高珪素鋼板およびその製造方法
JPH03207815A (ja) * 1990-01-04 1991-09-11 Nippon Steel Corp 冷間加工性および磁気特性の良好な高珪素軟磁性鋼板の製造方法
EP0526834A1 (fr) * 1991-07-29 1993-02-10 Nkk Corporation Procédé pour la fabrication de bandes d'acier au silicium ayant une granulation fine disposée en orientation de GOSS

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PATENT ABSTRACTS OF JAPAN vol. 7, no. 95 (C - 163) 23 August 1983 (1983-08-23) *
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10760143B2 (en) 2015-09-17 2020-09-01 Jfe Steel Corporation High-silicon steel sheet and method of manufacturing the same

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DE69312233T2 (de) 1997-12-18
KR940014852A (ko) 1994-07-19
CN1089663A (zh) 1994-07-20
CN1035889C (zh) 1997-09-17
DE69312233D1 (de) 1997-08-21
KR960006447B1 (ko) 1996-05-16
EP0601549B1 (fr) 1997-07-16

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