Patent Application
20250087396
This application relates to a wound core and a method for producing the wound core and more particularly to a wound core for a transformer produced using a grain-oriented electrical steel sheet as a material and a method for producing the wound core.
A grain-oriented electrical steel sheet with a crystal structure in which a <001> orientation, which is an easy axis of magnetization of iron, is highly aligned in the rolling direction of the steel sheet is particularly used as an iron core material for a power transformer. Depending on their core structures, transformers are broadly divided into stacked core transformers and wound core transformers. In a stacked core transformer, steel sheets cut into a predetermined shape are stacked to form an iron core. On the other hand, in a wound core transformer, a steel sheet is wound to form an iron core. Although there are various requirements for transformer cores, the most important requirement is low iron loss.
From this perspective, it is important that a grain-oriented electrical steel sheet, which is an iron core material, also has low iron loss characteristics. Furthermore, to reduce the excitation current and the copper loss in a transformer, a high magnetic flux density is also required. The magnetic flux density is evaluated by the magnetic flux density B8 (T) at a magnetizing force of 800 A/m. In general, B8 increases with the degree of accumulation in the Goss orientation. An electrical steel sheet with a high magnetic flux density typically has low hysteresis loss and good iron loss characteristics. To reduce the iron loss, it is important to highly align the crystal orientation of secondary recrystallized grains in a steel sheet with the Goss orientation and to reduce impurities in the steel components.
However, there is a limit to the control of crystal orientation and the reduction of impurities. Thus, a technique of introducing nonuniformity into the surface of a steel sheet by a physical method and refining the width of a magnetic domain to reduce the iron loss, that is, a magnetic domain refining technique has been developed. For example, Patent Literature 1 and Patent Literature 2 describe a heat-resistant magnetic domain refining method of providing a linear groove with a predetermined depth on the surface of a steel sheet. Patent Literature 1 describes a means for forming a groove with a gear roller. Patent Literature 2 describes a means for forming a linear groove on the surface of a steel sheet by etching. These means have the advantage that even when heat treatment, such as strain relief annealing, at the time of forming a wound core does not eliminate the magnetic domain refining effect applied to a steel sheet and that they are applicable to a wound core and the like.
To reduce the transformer iron loss, it is generally considered that the iron loss (material iron loss) of a grain-oriented electrical steel sheet as an iron core material should be reduced. On the other hand, the iron loss in a transformer is often higher than the material iron loss. A value obtained by dividing the iron loss (transformer iron loss) when an electrical steel sheet is used as an iron core of a transformer by the iron loss of a material obtained by an Epstein test or the like is generally called a building factor (BF) or a destruction factor (DF). In a transformer, BF is typically more than 1, and when BF can be reduced, the transformer iron loss can be reduced.
As a general knowledge, magnetic flux concentration in the inner side of an iron core caused by the difference in magnetic path length, generation of in-plane eddy-current loss at a steel sheet joint, an increase in iron loss due to the introduction of strain during processing, and the like are pointed out as factors (BF factors) for which the transformer iron loss in a wound core transformer increases with respect to the material iron loss.
The increase in iron loss due to the magnetic flux concentration in the inner side of an iron core caused by the difference in magnetic path length is described below. In a single-phase wound core illustrated in
The generation of in-plane eddy-current loss at a steel sheet joint is described below. In general, in a wound core for a transformer, a cut portion is provided to insert a winding wire. After the winding wire is inserted from the cut portion into the iron core, steel sheets are provided with a lap portion and are joined together. As illustrated in
The introduction of strain during processing also causes an increase in iron loss. Strain introduced by slitting of a steel sheet, bending at the time of processing an iron core, or the like impairs the magnetic characteristics of a steel sheet and increases the transformer iron loss. A wound core is typically subjected to annealing at a temperature above the strain relief temperature, that is, so-called strain relief annealing, after iron core processing.
In view of such an increasing factor of the transformer iron loss, for example, the following proposals have been made as measures to reduce the transformer iron loss.
Patent Literature 3 discloses that an electrical steel sheet with magnetic characteristics poorer than the outer circumferential side is arranged on the inner circumferential side of an iron core with a short magnetic path length, and an electrical steel sheet with magnetic characteristics better than the inner circumferential side is arranged on the outer circumferential side of the iron core with a long magnetic path length, thereby avoiding magnetic flux concentration on the inner circumferential side of the iron core and effectively reducing the transformer iron loss. Patent Literature 4 discloses an iron core design method of combining a plurality of types of electrical steel sheets with different magnetic permeabilities and iron losses to control the magnetic flux concentration and the iron loss deterioration caused by the concentration and reduce the transformer iron loss.
As disclosed in Patent Literature 3 and Patent Literature 4, to avoid the magnetic flux concentration in the inner circumferential side of an iron core, different materials for the inner circumferential side and the outer circumferential side of the iron core can be used to efficiently improve transformer characteristics. However, these methods require two types of materials with different magnetic characteristics (iron loss) to be appropriately arranged and therefore complicate the design of a transformer and remarkably reduce the productivity thereof.
An object of the disclosed embodiments is to provide a wound core with low transformer iron loss and good magnetic characteristics without using two or more types of materials with different magnetic characteristics and a method for producing the wound core.
To produce a wound core with low transformer iron loss and good magnetic characteristics, it is necessary to design an iron core to reduce the magnetic flux concentration and to select an iron core material that can reduce the increase in iron loss even when a magnetic flux is concentrated in the inner side of the iron core.
The following three points are required for the iron core design to reduce magnetic flux concentration.
(1) A wound core should have a flat surface portion, a corner portion adjacent to the flat surface portion, a lap portion in the flat surface portion, and a bent portion in the corner portion.
(2) A grain-oriented electrical steel sheet with a magnetic flux density B8 of 1.91 T or less at a magnetic field strength H of 800 A/m should be used as an iron core material.
(3) The ratio of the length of the outer circumference to the length of the inner circumference of an iron core (the length of the outer circumference/the length of the inner circumference) should be 1.80 or less.
Furthermore, the following points are necessary for selecting an iron core material that can suppress the increase in iron loss even when a magnetic flux is concentrated in the inner side of the iron core.
(4) A grain-oriented electrical steel sheet should have a magnetic flux density B8 of 1.84 T or more at a magnetic field strength H of 800 A/m.
(5) A grain-oriented electrical steel sheet should have an iron loss deterioration rate of 1.50 or less under compressive stress as calculated using the following formula:
Iron loss deterioration rate under compressive stress=(iron loss at a compressive stress of 5 MPa)/(iron loss under no compressive stress)
wherein the iron loss at a compressive stress of 5 MPa and the iron loss under no compressive stress are the iron loss (W/kg) measured at a frequency of 50 Hz and at a maximum magnetization of 1.7 T, and the iron loss at a compressive stress of 5 MPa is the iron loss measured at a compressive stress of 5 MPa in the rolling direction of an iron core material.
These requirements and the reasons for the requirements are described in detail below.
(1) A wound core should have a flat surface portion, a corner portion adjacent to the flat surface portion, a lap portion in the flat surface portion, and a bent portion in the corner portion.
The wound core is produced by winding a magnetic material, such as a grain-oriented electrical steel sheet. In a typical method, a steel sheet is wound into a cylindrical shape, is then pressed such that a corner portion has a certain curvature, and is formed into a rectangular shape. On the other hand, in another production method, a portion to be a corner portion of a wound core is bent in advance, and the bent steel sheets are lapped to form the wound core. The iron core formed by this method has a bend (bent portion) at a corner portion. The iron core formed by the former method is generally referred to as a “tranco-core”, and the iron core formed by the latter method is generally referred to as a “unicore” or a “duocore” depending on the number of steel sheet joints provided. To reduce the magnetic flux concentration, a structure with a bend (bent portion) at a corner portion formed by the latter method is suitable.
The results of experimental investigation of the magnetic flux concentration in iron cores of a tranco-core and a unicore are described below. Iron cores of a single-phase tranco-core and two unicores with the shape illustrated in
The following is a possible reason for the lower magnetic flux concentration due to the unicore, that is, due to the bent portion provided at the corner portion. In the bent portion of the unicore, deformation twin and the like remain even after strain relief annealing, and the magnetic permeability is locally lower than the other portion. In the presence of a portion with significantly low magnetic permeability, a magnetic flux of a certain level or higher cannot pass through the portion. Thus, even a difference in magnetic path length exists, it rarely causes magnetic flux concentration only in the inner side of the iron core. It is assumed that the inner winding portion of the unicore has lower magnetic flux concentration than the tranco-core without a bent portion of low magnetic permeability.
(2) A grain-oriented electrical steel sheet with a magnetic flux density B8 of 1.91 T or less at a magnetic field strength H of 800 A/m should be used as an iron core material.
The results of experimental investigation of the effects of the magnetic flux density B8 on magnetic flux concentration inside an iron core of a unicore are described below. A single-phase unicore with the shape illustrated in
The following is a possible reason why the magnetic flux concentration in the iron core decreases as the magnetic flux density B8 of the grain-oriented electrical steel sheet as a material decreases. A large amount of magnetic flux can typically pass through an iron core material with a high magnetic flux density B8. It is thought that magnetic flux concentration in the inner side of an iron core material with a high magnetic flux density B8 is likely to occur due to the difference in magnetic path length. In contrast, only a certain amount of magnetic flux can pass through an iron core material with a low magnetic flux density B8. Thus, even a difference in magnetic path length exists, it rarely causes magnetic flux concentration only in the inner side of the iron core. In other words, it is assumed that magnetic flux concentration in an iron core is lower in an iron core material with a low magnetic flux density B8 than in an iron core material with a high magnetic flux density B8.
(3) The ratio of the length of the outer circumference to the length of the inner circumference of an iron core (the length of the outer circumference/the length of the inner circumference) should be 1.80 or less.
The results of experimental investigation of the effects of the difference in magnetic path length between the inner side and the outer side of an iron core on the magnetic flux concentration are described below. An iron core with the shape shown in
Next, the conditions and reasons for the selection of an iron core material that reduces the increase in iron loss when a magnetic flux is concentrated in the inner side of an iron core are described below.
(4) A grain-oriented electrical steel sheet should have a magnetic flux density B8 of 1.84 T or more at a magnetic field strength H of 800 A/m.
In general, the iron loss of a magnetic material increases nonlinearly and rapidly as the saturation magnetization is approached with respect to the increase in the excitation magnetic flux density. Thus, when a magnetic flux is concentrated in the inner side of an iron core and the magnetic flux density is locally increased, as described above, the iron loss is higher than the case of a uniform magnetic flux density distribution. From the perspective of saturation magnetization, as the saturation magnetization increases, the nonlinear increase in iron loss can be reduced, and the increase in iron loss can therefore be reduced. Although saturation magnetization in an electrical steel sheet depends mainly on the Si content, the magnetic flux density B8 of an iron core material is effective for an increase in iron loss in a practical excitation magnetic flux density region. The results of experimental investigation of the effects of the magnetic flux density B8 of an iron core material on the iron loss of a unicore are described below. A single-phase unicore with the shape illustrated in
(5) A grain-oriented electrical steel sheet should have an iron loss deterioration rate of 1.50 or less under compressive stress.
The inner side of an iron core, where the magnetic flux is concentrated and the iron loss increases, is a portion in which strain due to processing is likely to remain. In general, residual strain disturbs the magnetic domain structure of the portion, impairs magnetic permeability, and increases the iron loss of the entire iron core. Furthermore, when strain relief annealing is performed after processing, twinning is present in a rectangular bent portion and, in the same manner as in residual strain, disturbs the magnetic domain structure of the portion, impairs magnetic permeability, and increases the iron loss of the entire iron core. Thus, reducing the increase in iron loss due to residual strain and twinning can reduce the increase in iron loss even when magnetic flux is concentrated in the inner side of an iron core.
As a result of searching for an iron core material that can reduce the increase in iron loss due to residual strain and twinning, it was found that the iron loss in a transformer core can be reduced by selecting a material with an iron loss deterioration rate of 1.50 or less under compressive stress.
The experimental results on which the above preferred ranges are based are described below. A single-phase unicore with the shape illustrated in
Iron loss deterioration due to magnetic domain disturbance caused by compressive stress is correlated with the increase in iron loss due to residual strain and twinning in a wound core. Thus, it is assumed that, even when a magnetic flux is concentrated in the inner side of an iron core, the increase in iron loss can be reduced by selecting an iron core material on the basis of the iron loss deterioration rate under compressive stress.
The disclosed embodiments have been made on the basis of these findings and have the following constitution.
[1]A wound core comprising a grain-oriented electrical steel sheet as a material, wherein
Iron loss deterioration rate under compressive stress=(iron loss at a compressive stress of 5 MPa)/(iron loss under no compressive stress)
[2] The wound core according to [1], wherein the grain-oriented electrical steel sheet is subjected to heat-resistant magnetic domain refining treatment.
[3]A method for producing a wound core that is composed of a grain-oriented electrical steel sheet as a material and has a flat surface portion, a corner portion adjacent to the flat surface portion, a lap portion in the flat surface portion, and a bent portion in the corner portion, wherein
Iron loss deterioration rate under compressive stress=(iron loss at a compressive stress of 5 MPa)/(iron loss under no compressive stress)
[4] The method for producing a wound core according to [3], wherein the grain-oriented electrical steel sheet is subjected to heat-resistant magnetic domain refining treatment.
The disclosed embodiments can provide a wound core with low transformer iron loss and good magnetic characteristics and a method for producing the wound core. The disclosed embodiments can provide a wound core with low transformer iron loss and good magnetic characteristics without using two or more types of materials with different magnetic characteristics (iron loss). The disclosed embodiments can provide a wound core with low iron loss and good magnetic characteristics with high productivity while reducing the complexity of iron core design, such as the arrangement of materials required when two or more types of materials with different magnetic characteristics are used.
The disclosed embodiments are described in detail below.
As described above, to provide a transformer wound core with low iron loss, the following conditions should be satisfied.
(A) A wound core should have a flat surface portion, a corner portion adjacent to the flat surface portion, a lap portion in the flat surface portion, and a bent portion in the corner portion.
(B) The ratio of the length of the outer circumference to the length of the inner circumference of an iron core is 1.80 or less.
(A) is satisfied by selecting a method of producing a wound core generally called a unicore or duocore type. A known method may be employed as a method for producing a wound core. More specifically, a unicore producing machine manufactured by AEM Cores Pty Ltd can be used to read the design size, thereby shearing and bending a steel sheet in the size according to the design drawing to produce a processed steel sheet one by one, and the processed steel sheets can be stacked to produce a wound core.
The lengths of the outer circumference and the inner circumference of an iron core in the condition (B) refer to the length of the outer circumference and the length of the inner circumference of the iron core, respectively, when the iron core is viewed from the side. Thus, when an iron core is viewed from the side, the length of the outer circumference of the iron core is the length of one turn in the winding direction of a grain-oriented electrical steel sheet (material) constituting a wound core along the outside (outer surface) of the outermost grain-oriented electrical steel sheet, and the length of the inner circumference of the iron core is the length of one turn in the winding direction of a grain-oriented electrical steel sheet constituting the wound core along the inside (inner surface) of the innermost grain-oriented electrical steel sheet. The upper limit of the ratio of the length of the outer circumference to the length of the inner circumference of an iron core should be 1.80. The ratio is preferably 1.70 or less, more preferably 1.60 or less. The lower limit of the ratio is not particularly defined in terms of characteristics and is determined by the relationship between the iron core size and the thickness because the iron core thickness decreases as the ratio approaches 1. For example, the lower limit of the ratio is 1.05.
As long as the requirements (A) and (B) are controlled within the scope of the disclosed embodiments, there are no particular limitations on the type of steel sheet joint, the iron core size, the bending angle of a bent portion, the number of bent portions, and the like other than (A) and (B).
As described above, to provide a transformer wound core with low iron loss, the following conditions should be satisfied.
(C) A grain-oriented electrical steel sheet with a magnetic flux density B8 in the range of 1.84 T to 1.91 T at a magnetic field strength H of 800 A/m should be used as an iron core material.
The magnetic characteristics are measured by the Epstein test. The Epstein test is performed by a known method, such as IEC standard or JIS standard. Alternatively, when it is difficult to evaluate the magnetic flux density B8 by the Epstein test, for example, in the case of a non-heat-resistant magnetic domain refined material, the results of a single sheet tester (SST) may be used instead. In the production of a wound core, a representative characteristic of a grain-oriented electrical steel sheet coil should be used for selection in accordance with the preferred range of the magnetic flux density B8. More specifically, a test sample is taken at the front and rear ends of a steel sheet coil and is subjected to the Epstein test to measure the magnetic flux density B8, and the average value thereof is adopted as a representative characteristic. Alternatively, the material may be selected on the basis of a characteristic value (an average value and a guaranteed value) of a steel sheet provided by a steel manufacturer. The magnetic flux density B8 is preferably 1.86 T or more.
(D) A grain-oriented electrical steel sheet with an iron loss deterioration rate of 1.50 or less under compressive stress as calculated using the following formula is used as an iron core material.
Iron loss deterioration rate under compressive stress=(iron loss at a compressive stress of 5 MPa)/(iron loss under no compressive stress)
The iron loss at a compressive stress of 5 MPa and the iron loss under no compressive stress defined in the above formula are the iron loss (W/kg) measured with a single sheet tester at a frequency of 50 Hz and at a maximum magnetization of 1.7 T, and the iron loss at a compressive stress of 5 MPa is the iron loss measured at a compressive stress of 5 MPa in the rolling direction of a grain-oriented electrical steel sheet serving as an iron core material. The compressive stress is applied to the compression side at 5 MPa uniaxially in the rolling direction of a steel sheet. The method of applying the compressive stress is, for example, but not limited to, a method of applying stress with a pusher or the like from one side of a steel sheet while fixing the opposite side with a clamp or the like. In such a case, the stress should be uniformly applied in the rolling direction so that the steel sheet does not buckle. To prevent buckling, the steel sheet may be fixed from upper side and from lower side of the sheet in the direction perpendicular to the surface as long as it does not interfere with the measurement. The iron loss under no compressive stress is the iron loss measured without applying the compressive stress. In the disclosed embodiments, as described above, a grain-oriented electrical steel sheet with an iron loss deterioration rate of 1.50 or less under compressive stress is used as an iron core material. The iron loss deterioration rate under compressive stress is preferably 1.45 or less. The lower limit of the iron loss deterioration rate under compressive stress is, for example, but not limited to, 1.05.
As long as the requirements (C) and (D) are controlled within the scope of the disclosed embodiments, there are no particular limitations on the characteristics, components, production method, and the like of a grain-oriented electrical steel sheet other than (C) and (D).
Components and a production method of a grain-oriented electrical steel sheet suitable as a material for a wound core according to the disclosed embodiments are described below.
In the disclosed embodiments, a chemical composition of a slab for a grain-oriented electrical steel sheet may be a chemical composition that causes secondary recrystallization. When an inhibitor is used, for example, when an AlN inhibitor is used, appropriate amounts of Al and N may be contained, and when a MnS MnSe inhibitor is used, appropriate amounts of Mn and Se and/or S may be contained. As a matter of course, both inhibitors may be used in combination. In such a case, the preferred Al, N, S, and Se contents are Al: 0.010% to 0.065% by mass, N: 0.0050% to 0.0120% by mass, S: 0.005% to 0.030% by mass, and Se: 0.005% to 0.030% by mass.
The disclosed embodiments can also be applied to an inhibitor-free grain-oriented electrical steel sheet with limited Al, N, S, and Se contents. In such a case, the amounts of Al, N, S, and Se are preferably reduced to Al: 100 ppm by mass or less, N: 50 ppm by mass or less, S: 50 ppm by mass or less, and Se: 50 ppm by mass or less.
Base components and optional additive components of the slab for a grain-oriented electrical steel sheet are specifically described below.
C is added to improve the microstructure of a hot-rolled steel sheet. However, a C content of more than 0.08% by mass makes it difficult to reduce the C content to 50 ppm by mass or less at which magnetic aging does not occur in the production process, so that the C content is preferably 0.08% by mass or less. The C content has no particular lower limit because secondary recrystallization is possible even in a material containing no C. Thus, the C content may be 0% by mass.
Si is an element effective in increasing the electrical resistance of steel and improving iron loss. At a Si content of 2.0% by mass or more, a sufficient iron loss reducing effect is more easily obtained. On the other hand, at a Si content of 8.0% by mass or less, a significant decrease in workability can be suppressed, and a decrease in magnetic flux density can also be easily suppressed. Thus, the Si content preferably ranges from 2.0% to 8.0% by mass.
Mn is an element necessary for improving hot workability. At a Mn content of 0.005% by mass or more, the effect of addition thereof is easily obtained. On the other hand, at a Mn content of 1.000% by mass or less, the decrease in the magnetic flux density of a product sheet is easily suppressed. Thus, the Mn content preferably ranges from 0.005% to 1.000% by mass.
Cr is an element that promotes the formation of a dense oxide film at the interface between a forsterite film and a steel substrate. Although an oxide film can be formed without the addition of Cr, the addition of 0.02% by mass or more of Cr is expected to expand a preferred range of other components. At a Cr content of 0.20% by mass or less, an oxide film can be prevented from becoming too thick, and the deterioration of coating peeling resistance can be easily suppressed. Thus, the Cr content preferably ranges from 0.02% to 0.20% by mass.
The slab for a grain-oriented electrical steel sheet preferably contains these components as base components. In addition to these components, the slab may appropriately contain the following elements.
At least one selected from Ni: 0.03% to 1.50% by mass, Sn: 0.010% to 1.500% by mass, Sb: 0.005% to 1.500% by mass, Cu: 0.02% to 0.20% by mass, P: 0.03% to 0.50% by mass, and Mo: 0.005% to 0.100% by mass
Ni is an element useful for improving the microstructure of a hot-rolled steel sheet and improving magnetic characteristics. At a Ni content of 0.03% by mass or more, the effect of improving the magnetic characteristics is more easily obtained. At a Ni content of 1.50% by mass or less, it is possible to suppress secondary recrystallization from becoming unstable, and it is easy to reduce the possibility that the magnetic characteristics of a product sheet deteriorate. Thus, when Ni is contained, the Ni content preferably ranges from 0.03% to 1.50% by mass.
Sn, Sb, Cu, P, and Mo are elements useful for improving the magnetic characteristics, and at a content thereof above their respective lower limits, the effect of improving the magnetic characteristics is more easily obtained. On the other hand, at a content thereof below their respective upper limits, it is easy to reduce the possibility that the development of secondary recrystallized grains is inhibited. Thus, when Sn, Sb, Cu, P, and Mo are contained, each element content is preferably within the above range.
The remainder other than these components is composed of incidental impurities in the production process and Fe.
Next, a production method of a grain-oriented electrical steel sheet suitable as a material for a wound core according to the disclosed embodiments is described below.
A slab with the chemical composition described above is heated in the usual manner. The heating temperature preferably ranges from 1150° C. to 1450° C.
The heating is followed by hot rolling. After casting, hot rolling may be performed immediately without heating. A thin cast steel may be or may not be hot-rolled. For hot rolling, the rolling temperature in the final rough rolling pass is 900° C. or more, and the rolling temperature in the final finish rolling pass is 700° C. or more.
Subsequently, a hot-rolled steel sheet is annealed as required. To highly develop the Goss structure in the product sheet, the annealing temperature of the hot-rolled steel sheet preferably ranges from 800° C. to 1100° C. When the annealing temperature of the hot-rolled steel sheet is less than 800° C., the band microstructure in the hot rolling remains, and it is difficult to realize a primary recrystallization texture with a controlled grain size, and the development of secondary recrystallization may be inhibited. On the other hand, when the annealing temperature of the hot-rolled steel sheet is more than 1100° C., the grain size after annealing of the hot-rolled steel sheet becomes too coarse, so that it may be extremely difficult to realize a primary recrystallization texture with a controlled grain size.
Subsequently, cold rolling is performed once or twice or more with intermediate annealing interposed therebetween. The intermediate annealing temperature preferably ranges from 800° C. to 1150° C. The intermediate annealing time preferably ranges from approximately 10 to 100 seconds.
Subsequently, decarburization annealing is performed. In the decarburization annealing, preferably, the annealing temperature ranges from 750° C. to 900° C., the oxidizing atmosphere PH2O/PH2 ranges from 0.25 to 0.60, and the annealing time ranges from approximately 50 to 300 seconds.
Subsequently, an annealing separator is applied. The annealing separator is preferably composed mainly of MgO and is preferably applied in an amount in the range of approximately 8 to 15 g/m2.
Subsequently, finish annealing is performed for the purpose of secondary recrystallization and the formation of a forsterite film. The annealing temperature is preferably 1100° C. or more, and the annealing time is preferably 30 minutes or more.
Subsequently, flattening treatment (flattening annealing) and insulating coating are performed. It is also possible to perform flattening treatment to correct the shape by the application and baking of insulating coating at the time of applying the insulating coating. The flattening annealing is preferably performed at an annealing temperature in the range of 750° C. to 950° C. for an annealing time in the range of approximately 10 to 200 seconds. In the disclosed embodiments, the insulating coating can be applied to the surface of a steel sheet before or after the flattening annealing. The term “insulating coating”, as used herein, refers to coating (tension coating) that applies tension to a steel sheet to reduce iron loss. The tension coating may be inorganic coating containing silica, ceramic coating by a physical vapor deposition method or a chemical vapor deposition method, or the like.
In general, the iron loss deterioration rate under compressive stress decreases as the tensile strength of a surface film (a forsterite film and insulating coating) applied to a steel sheet increases. Although the thickness of tension coating may be increased to increase film tension, the lamination factor may deteriorate. To obtain high tension without deterioration of the lamination factor, in an inorganic coating containing silica, the baking temperature may be increased to promote glass crystallization. The application of a film with a low thermal expansion coefficient, such as ceramic coating, is also effective in obtaining high tension.
To reduce the iron loss of a steel sheet, magnetic domain refining treatment is preferably performed. The magnetic domain refining technique is a technique of introducing nonuniformity into the surface of a steel sheet by a physical method and refining the width of a magnetic domain to reduce the iron loss. The magnetic domain refining technique is broadly divided into heat-resistant magnetic domain refining in which the effect is not lost in strain relief annealing and non-heat-resistant magnetic domain refining in which the effect is reduced by strain relief annealing. In the disclosed embodiments, it can be applied to any of a steel sheet not subjected to magnetic domain refining treatment, a steel sheet subjected to heat-resistant magnetic domain refining treatment, and a steel sheet subjected to non-heat-resistant magnetic domain refining treatment.
Among them, a steel sheet subjected to heat-resistant magnetic domain refining treatment is more preferred than a steel sheet subjected to non-heat-resistant magnetic domain refining treatment. The non-heat-resistant magnetic domain refining treatment is typically a treatment of irradiating a steel sheet after secondary recrystallization with a high-energy beam (a laser or the like) to introduce a high dislocation density region into a steel sheet surface layer and form a stress field associated therewith, thereby performing magnetic domain refining. Compressive stress applied to a non-heat-resistant magnetic domain refined material (a steel sheet subjected to non-heat-resistant magnetic domain refining treatment) disturbs the stress field due to energy beam irradiation, reduces the magnetic domain refining effect, and increases the iron loss due to compressive stress. Thus, a steel sheet subjected to heat-resistant magnetic domain refining treatment is preferred. The method of heat-resistant magnetic domain refining treatment may be a known technique of providing a linear groove of a predetermined depth on the surface of a steel sheet.
The disclosed embodiments will now be described more specifically with respect to the following examples. The examples are preferred examples of the disclosed embodiments, and this disclosure is not intended to be limited to these examples. It will be understood that disclosed embodiments may be appropriately modified within the scope of the gist of this disclosure and included in the technical scope of the disclosure.
A single-phase tranco-core and a single-phase unicore with an iron core shape shown in
Table 7 shows the results. It was found that the examples of the disclosed embodiments have better BF, lower transformer iron loss, and much better transformer characteristics than comparative examples. The examples using a heat-resistant magnetic domain refined material had particularly low transformer iron loss.
Tranco-
core A
Tranco-
core A
Tranco-
core B
Tranco-
core B
Tranco-
1.91
core C
Tranco-
1.91
core C
1.84
1.84
1.81
1.81
1.54
1.62
1.54
1.62
1.84
1.84
1.54
1.94
1.92
1.83
1.92
1.92
1.92
1.55
1.92
1.62
1.54
| Number | Date | Country | Kind |
|---|---|---|---|
| 2021-124863 | Jul 2021 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2022/023038 | 6/8/2022 | WO |
