WO2024106462A1 - 方向性電磁鋼板およびその製造方法 - Google Patents

方向性電磁鋼板およびその製造方法 Download PDF

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WO2024106462A1
WO2024106462A1 PCT/JP2023/041072 JP2023041072W WO2024106462A1 WO 2024106462 A1 WO2024106462 A1 WO 2024106462A1 JP 2023041072 W JP2023041072 W JP 2023041072W WO 2024106462 A1 WO2024106462 A1 WO 2024106462A1
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steel sheet
grain
annealing
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English (en)
French (fr)
Japanese (ja)
Inventor
隆史 片岡
龍太郎 山縣
まゆ子 菊月
潤紀 中村
嘉宏 諏訪
和年 竹田
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Nippon Steel Corp
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Nippon Steel Corp
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Priority to KR1020257015084A priority Critical patent/KR20250071287A/ko
Priority to EP23891609.2A priority patent/EP4621089A4/en
Priority to JP2024558916A priority patent/JPWO2024106462A1/ja
Priority to CN202380078743.8A priority patent/CN120265808A/zh
Publication of WO2024106462A1 publication Critical patent/WO2024106462A1/ja
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
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    • H01F1/147—Alloys characterised by their composition
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    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation

Definitions

  • the present disclosure relates to a grain-oriented electrical steel sheet and a manufacturing method thereof.
  • This application claims priority based on Japanese Patent Application No. 2022-182571, filed on November 15, 2022, the contents of which are incorporated herein by reference.
  • grain-oriented electrical steel sheet has a three-layer structure consisting of a base steel sheet, a primary coating (sometimes called a glass coating) formed on the surface of the base steel sheet, and a tension-applying insulating secondary coating formed on the surface of the primary coating.
  • Grain-oriented electrical steel sheet is a soft magnetic material, and is primarily used as a transformer core material. For this reason, grain-oriented electrical steel sheet is required to have magnetic properties such as high magnetization characteristics and low iron loss.
  • Iron loss is the power loss consumed as thermal energy when an iron core is excited by an alternating magnetic field, and from the perspective of energy conservation, it is desirable to have as low iron loss as possible.
  • the level of iron loss is affected by factors such as magnetic susceptibility, sheet thickness, coating tension, amount of impurities, electrical resistivity, crystal grain size, and magnetic domain size.
  • the iron loss of grain-oriented electrical steel sheet is the sum of eddy current loss, which depends on resistivity, sheet thickness, and size of magnetic domain, and hysteresis loss, which depends on crystal orientation and surface smoothness.
  • sheet thickness for example, making the base steel sheet thinner (for example, less than 0.22 mm) is effective in reducing iron loss by reducing eddy current loss.
  • making the sheet thinner will change the behavior of secondary recrystallization itself and degrade the degree of integration of the Goss orientation.
  • Goss orientation is manifested through a phenomenon (secondary recrystallization) that involves advanced control of the texture and precipitates (inhibitors). It is preferable that the texture has many Goss orientations (nuclei of secondary recrystallization) and many orientations (corresponding orientations) that are encroached upon by the Goss orientation. On the other hand, it is preferable that the pinning force of the inhibitor gradually decreases during secondary recrystallization annealing (the inhibitor has high heat resistance). In other words, a sudden decrease in the pinning force of the inhibitor during secondary recrystallization annealing is undesirable from the viewpoint of promoting the growth of the Goss orientation.
  • Patent Documents 1 and 2 disclose technology that avoids texture degradation by optimally controlling the cold rolling rate through pre-cold rolling.
  • Patent Document 3 discloses an inhibitor control technology through primary coating control.
  • MgO containing 0.15 to 2.0% Cl and/or SO 3 is applied as an annealing separator to significantly enhance the glass coating formation reaction and control the primary coating to a form favorable for magnetism.
  • Patent Documents 1 and 2 the number of cold rolling steps increases, which creates problems in production.
  • the method of Patent Document 3 allows inhibitor control, it does not take into consideration texture control. Therefore, for example, when this technology is applied to a thin electrical steel sheet having a base steel sheet thickness of less than 0.22 mm, it is highly likely that a high-quality secondary recrystallization orientation cannot be obtained.
  • the objective of this disclosure is to provide a grain-oriented electrical steel sheet that has good magnetic properties and noise characteristics without reducing productivity, and a method for manufacturing the same.
  • a method for producing a grain-oriented electrical steel sheet according to one embodiment of the present invention comprises, in mass%, C: 0.020 to 0.150%, Si: 3.00 to 4.00%, Sol.
  • the above aspects of the present disclosure make it possible to provide a grain-oriented electrical steel sheet and a manufacturing method thereof that have good magnetic properties and noise characteristics without reducing productivity.
  • the grain-oriented electrical steel sheet according to one embodiment of the present disclosure (grain-oriented electrical steel sheet according to this embodiment) comprises a base steel sheet having a predetermined chemical composition described later, a glass coating formed on the base steel sheet, and a tension-applying insulating coating formed on the glass coating.
  • the base steel sheet has a texture oriented in the Goss orientation.
  • the average dispersion angle from the ideal Goss orientation with the rolling surface normal direction ND as the rotation axis is defined as ⁇ (°)
  • the average dispersion angle from the ideal Goss orientation with the rolling transverse direction TD as the rotation axis is defined as ⁇ (°)
  • the average dispersion angle from the ideal Goss orientation with the rolling direction RD as the rotation axis is defined as ⁇ (°)
  • ⁇ , ⁇ , and ⁇ satisfy the following formula (1).
  • the grain-oriented electrical steel sheet according to this embodiment is described below.
  • FIG. 1A and 1B are diagrams that show a schematic structure of a grain-oriented electrical steel sheet according to this embodiment.
  • the grain-oriented electrical steel sheet 10 according to this embodiment has a base steel sheet 11, a primary coating (glass coating) 13 formed on the surface of the base steel sheet 11, and a secondary coating (tension-imparting insulating coating) 15, which is an example of an insulating coating, formed on the surface of the glass coating 13.
  • the glass coating 13 and the tension-imparting insulating coating 15 may be formed on at least one surface of the base steel sheet 11, but are usually formed on both surfaces of the base steel sheet 11, as shown typically in Fig. 1B.
  • the base steel sheet 11 exhibits excellent noise characteristics and magnetic characteristics by being manufactured from a steel billet containing the chemical components described in detail below. The chemical components of the base steel sheet 11 will be described in detail again below.
  • the glass coating 13 is an inorganic coating mainly composed of magnesium silicate, which is disposed on the surface of the base steel sheet 11.
  • the glass coating 13 is formed during finish annealing by a reaction between an annealing separator containing magnesia (MgO) applied to the surface of the base steel sheet and the components of the surface of the base steel sheet 11.
  • MgO magnesia
  • the glass coating 13 has a composition derived from the components of the annealing separator and the base steel sheet (more specifically, a composition mainly composed of Mg 2 SiO 4 ).
  • the tension-imparting insulating coating 15 is disposed on the surface of the glass coating 13.
  • the tension-imparting insulating coating 15 imparts electrical insulation to the grain-oriented electrical steel sheet 10, thereby reducing eddy current loss and improving the iron loss of the grain-oriented electrical steel sheet 10.
  • the tension-imparting insulating coating 15 also realizes various other properties, such as corrosion resistance, heat resistance, and slipperiness.
  • the tension-imparting insulating coating 15 has the function of imparting tension to the grain-oriented electromagnetic steel sheet 10.
  • the tension-imparting insulating coating 15 imparts tension to the grain-oriented electromagnetic steel sheet 10, facilitating domain wall movement in the grain-oriented electromagnetic steel sheet 10, thereby improving the iron loss of the grain-oriented electromagnetic steel sheet 10.
  • the tension-imparting insulating coating 15 is formed, for example, by applying a coating liquid whose main components are metal phosphate and silica to the surface of the glass coating 13 and baking it.
  • the thickness of the base steel sheet of the grain-oriented electrical steel sheet 10 according to this embodiment is not particularly limited, and can be, for example, 0.16 mm or more and 0.30 mm or less.
  • the thickness t of the base steel sheet of the grain-oriented electrical steel sheet 10 is, for example, less than 0.20 mm.
  • the lower limit of the thickness t may be 0.16 mm or more, or may be 0.17 mm or more.
  • the contents of the components other than carbon (C), acid-soluble aluminum (sol. Al), nitrogen (N), sulfur (S), and bismuth (Bi) in the base steel sheet 11 are maintained at the same contents as in the steel piece.
  • the contents of the components other than carbon (C), acid-soluble aluminum (sol. Al), nitrogen (N), and sulfur (S) in the base steel sheet 11 are approximately the same when it is a steel piece and when it is a product sheet.
  • the silicon (Si), manganese (Mn), chromium (Cr), boron (B), and titanium (Ti) in the base steel sheet 11 may be absorbed into the glass coating during manufacturing, resulting in a slight decrease in their content compared to their composition in the steel piece.
  • C 0.020 to 0.150%
  • C (carbon) is an element that has the effect of increasing magnetic flux density. If the C content of the steel piece is less than 0.020%, the effect of improving the magnetic flux density cannot be obtained. Therefore, the C content of the steel piece is set to 0.020% or more.
  • the C content is preferably 0.040% or more, and more preferably 0.050% or more.
  • the C content of the steel slab exceeds 0.150%, the steel undergoes a phase transformation during secondary recrystallization annealing (i.e., finish annealing), and secondary recrystallization does not proceed sufficiently, resulting in failure to obtain good magnetic flux density and iron loss characteristics. Therefore, the C content of the steel slab is set to 0.150% or less.
  • the lower the C content the more favorable it is for reducing iron loss. From the viewpoint of reducing iron loss, the C content is preferably 0.120% or less, and more preferably 0.100% or less.
  • the C content in the above-mentioned steel piece becomes the grain-oriented electrical steel sheet 10 according to this embodiment through the process described in detail below, so that the C content in the base steel sheet 11 is 0.010% (100 ppm) or less.
  • the C content in the base steel sheet 11 may be 0%. However, since it is difficult to achieve a C content of 0% in practical steel sheets from a manufacturing perspective, the C content may be greater than 0%.
  • Si 3.00 to 4.00%
  • Silicon (Si) is an extremely effective element for increasing the electrical resistance (resistivity) of steel and reducing eddy current loss, which constitutes part of iron loss. If the Si content of the steel slab is less than 3.00%, the steel undergoes phase transformation during secondary recrystallization annealing, and secondary recrystallization does not proceed sufficiently, making it difficult to obtain good magnetic flux density and iron loss characteristics. Therefore, the Si content of the steel slab is set to 3.00% or more.
  • the Si content of the steel slab is preferably 3.10% or more, and more preferably 3.20% or more.
  • the Si content of the steel slab is set to 4.00% or less.
  • the Si content of the steel slab is preferably 3.80% or less, and more preferably 3.50% or less.
  • the Si content in the above-mentioned steel piece may decrease as it becomes the grain-oriented electrical steel sheet 10 according to this embodiment through the process described in detail below.
  • the Si content in the base steel sheet 11 may decrease slightly as Si is consumed as a glass coating.
  • the amount of decrease is within a range that does not impede the action and effect of this embodiment, and the effect of this embodiment can be enjoyed by setting the Si content of the steel piece within the above range.
  • the Si content of the base steel sheet 11 may be 2.80 to 3.80%.
  • sol. Al 0.010 to 0.050%
  • Al (acid-soluble aluminum) is a constituent element of a major inhibitor among compounds called inhibitors that affect secondary recrystallization in grain-oriented electrical steel sheets. Al is an essential element from the viewpoint of recrystallization. If the sol. Al content of the steel slab is less than 0.010%, AlN, which functions as an inhibitor, is not sufficiently generated, and secondary recrystallization is insufficient. Therefore, the sol. Al content in the steel slab is set to 0.010% or more, and preferably 0.020% or more. On the other hand, if the sol. Al content exceeds 0.050%, embrittlement of the steel sheet becomes significant. Therefore, the sol. Al content of the steel slab is set to 0.050% or less. The amount is preferably 0.040% or less, more preferably 0.030% or less.
  • the sol. Al content in the above-mentioned steel slab becomes 0.010% (100 ppm) or less in the base steel sheet 11 after going through the process described in detail below to become the grain-oriented electrical steel sheet 10 according to this embodiment.
  • the lower limit of the sol. Al content in the base steel sheet 11 is not particularly limited, so it may be 0%.
  • Mn 0.01 to 0.50%
  • Mn manganese
  • Mn manganese
  • MnS manganese
  • the Mn content is preferably 0.03% or more, and more preferably 0.06% or more.
  • the Mn content of the steel slab exceeds 0.50%, the steel undergoes a phase transformation during secondary recrystallization annealing, and secondary recrystallization does not proceed sufficiently, making it difficult to obtain good magnetic flux density and iron loss characteristics. Therefore, the Mn content of the steel slab is set to 0.50% or less.
  • the Mn content is preferably 0.20% or less, and more preferably 0.10% or less.
  • the Mn content in the above-mentioned steel piece may decrease as it becomes the grain-oriented electrical steel sheet 10 according to this embodiment through the process described in detail below.
  • the Mn content in the base steel sheet 11 may decrease slightly due to Mn absorption in the glass coating.
  • the amount of decrease is within a range that does not impede the action and effect of this embodiment, and the effect of this embodiment can be enjoyed by setting the Mn content of the steel piece within the above range.
  • the Mn content of the base steel sheet 11 may be 0 to 0.40%.
  • N is an element that reacts with the above-mentioned acid-soluble Al to form AlN that functions as an inhibitor. Since N combines with Al to form AlN that functions as an inhibitor, the N content of the steel slab is set to 0.001% or more. The N content is preferably 0.004% or more, and more preferably 0.006% or more. On the other hand, if the N content of the steel slab exceeds 0.020%, blisters (voids) are formed in the steel sheet during cold rolling, and the strength increases, deteriorating the sheet passability during production. Therefore, the N content of the steel slab is set to 0.020% or less. The N content is preferably 0.015% or less, and more preferably 0.010% or less.
  • the N content in the above-mentioned steel piece becomes the grain-oriented electrical steel sheet 10 according to this embodiment through the process described in detail below, so that the N content in the base steel sheet 11 becomes 0.010% (100 ppm) or less.
  • the lower limit of the N content in the base steel sheet 11 is not particularly limited, so it may be 0%.
  • S + Se 0.0010 to 0.0400%
  • S (sulfur) and Se (selenium) are important elements that react with the above-mentioned Mn to form MnS or MnSe, which are inhibitors. If the total of the S content and Se content of the steel slab is less than 0.0010%, a sufficient inhibitor effect cannot be obtained. Therefore, the total of the S content and Se content of the steel slab is set to 0.0010% or more.
  • the total of the S content and Se content is preferably 0.0100% or more, and more preferably 0.0150% or more.
  • the total of the S content and the Se content of the steel slab exceeds 0.0400%, this causes hot brittleness and makes hot rolling extremely difficult. Therefore, the total of the S content and the Se content of the steel slab is set to 0.0400% or less.
  • the total of the S content and the Se content is preferably 0.0300% or less.
  • the S content in the above-mentioned steel slab may decrease as it becomes the grain-oriented electrical steel sheet 10 according to this embodiment through the process described in detail below.
  • the S content in the base steel sheet 11 may be 0.0100% (100 ppm) or less.
  • the lower limit of the total S content and Se content in the base steel sheet 11 is not particularly limited and may be 0.0005%.
  • the lower limit of the total S content and Se content in the base steel sheet 11 may include 0%. Note that it is necessary to pay close attention to the identification of S or Se of less than 0.0005%.
  • the total S content and Se content may be considered to be 0%. In practical steel sheets, the lower limit of the actual total S content and Se content is 0.0005%.
  • P 0.005 to 0.100%
  • P phosphorus
  • the P content of the steel slab is set to 0.005% or more, and preferably 0.010% or more.
  • P is an element that reduces workability in rolling. If the P content exceeds 0.100%, the rolling workability decreases, and there is a risk of the steel sheet breaking during production. Therefore, the P content is set to 0.100% or less.
  • the P content is preferably set to 0.070% or less, and more preferably set to 0.030% or less.
  • the chemical composition of the steel slab and base steel sheet 11 according to this embodiment basically contains the above-mentioned elements (basic elements), with the balance being Fe and impurities.
  • one or more elements (optional elements) selected from the group consisting of Sn, Cu, Cr, Sb, Mo, Ni, Nb, B, Ti, and Bi may be further contained in the ranges shown below. Since Sn, Cu, Cr, Sb, Mo, Ni, Nb, B, Ti, and Bi are optional elements in the steel slab and base steel sheet 11 according to this embodiment, the lower limit of their content is 0%.
  • Sn 0 to 0.50%
  • Sn (tin) is an element that has a magnetic property improving effect. Therefore, it may be contained.
  • the Sn content is 0.01% or more in order to exhibit the magnetic property improving effect well.
  • the Sn content is more preferably 0.03% or more.
  • the Sn content is set to 0.50% or less.
  • the Sn content is preferably 0.40% or less, and more preferably 0.30% or less.
  • Cu 0 to 0.50%
  • Cu (copper) is an element that contributes to increasing the Goss orientation occupancy rate in the secondary recrystallized structure and also contributes to improving the glass coating adhesion.
  • the Cu content is preferably 0.01% or more.
  • the Cu content is more preferably 0.05% or more.
  • the Cu content of the steel slab is set to 0.50% or less.
  • the Cu content is preferably 0.40% or less, and more preferably 0.30% or less.
  • Cr 0 to 0.50%
  • Cr chromium
  • the Cr content is preferably 0.01% or more.
  • the Cr content is more preferably 0.03% or more.
  • the Cr content is set to 0.50% or less.
  • the Cr content is preferably 0.40% or less, and more preferably 0.30% or less.
  • Sb 0 to 0.20%
  • Sb antimony
  • the content is preferably 0.01% or more in order to exhibit the magnetic property improving effect well.
  • the upper limit of the Sb content is set to 0.20%.
  • the Sb content is preferably 0.15% or less, and more preferably 0.10% or less.
  • Mo 0 to 0.10%
  • Mo molybdenum
  • Mo is an element that has a magnetic property improving effect. Therefore, it may be contained.
  • Mo molybdenum
  • the Mo content exceeds 0.10%, the cold rolling property deteriorates and there is a possibility of fracture. Therefore, if Mo is contained, the Mo content is set to 0.10% or less.
  • the Mo content is preferably 0.05% or less, and more preferably 0.03% or less.
  • Ni 0 to 0.20%
  • Ni nickel
  • Ni (nickel) is an effective element for affecting the crystal orientation rotation that occurs during cold rolling and obtaining a texture that is favorable for secondary recrystallization. It is also an effective element for increasing resistivity and reducing iron loss. Therefore, it may be contained.
  • the Ni content is 0.01% or more in order to obtain these effects.
  • the Ni content exceeds 0.20%, the secondary recrystallization may become unstable. Therefore, if Ni is contained, the Ni content is set to 0.20% or less.
  • the Ni content is preferably 0.15% or less, and more preferably 0.10% or less.
  • Nb 0 to 0.0200%
  • Nb niobium
  • the Nb content is preferably 0.0005% or more.
  • the Nb content is more preferably 0.0010% or more.
  • the Nb content is set to 0.0200% or less.
  • the Nb content is preferably 0.0100% or less, and more preferably 0.0050% or less.
  • B 0 to 0.0200%
  • B is an element that is effective in strengthening the inhibitor action and stably obtaining secondary recrystallization. Therefore, it may be contained.
  • the B content is preferably 0.0005% or more.
  • the B content is more preferably 0.0010% or more.
  • the B content is set to 0.0200% or less.
  • the B content is preferably 0.0100% or less, and more preferably 0.0050% or less.
  • Ti 0 to 0.0200%
  • Ti titanium is an element that increases the degree of accumulation of Goss orientation and improves magnetic properties. Although the cause is unclear, it may combine with N to form TiN and function as an inhibitor.
  • the Ti content is set to 0.0005% or more, preferably 0.0010% or more.
  • the Ti content is set to 0.0200% or less, preferably 0.0100% or less, and more preferably 0.0050% or less.
  • Bi 0 to 0.0200%
  • Bi bismuth
  • the Bi content is set to 0.0010% or more, and preferably 0.0020% or more.
  • the Bi content is set to 0.0200% or less, preferably 0.0100% or less.
  • the Bi content in the above-mentioned steel slab becomes the grain-oriented electrical steel sheet 10 according to this embodiment through the process described in detail below, so that the Bi content in the base steel sheet 11 becomes 0.0100% (100 ppm) or less.
  • the lower limit of the Bi content in the base steel sheet 11 is not particularly limited, so it may be 0%. It may also be more than 0%.
  • the Cr, B, and Ti contents in the above-mentioned steel piece may decrease as it becomes the grain-oriented electrical steel sheet 10 according to this embodiment through the process described in detail below.
  • the contents of these elements in the base steel sheet 11 may decrease slightly as a result of Cr being absorbed in the glass coating, or inclusions such as BN and TiN being formed.
  • the amount of decrease is within a range that does not affect the effect of this embodiment.
  • the total amount of chemical components in the base steel sheet 11 can be obtained from the grain-oriented electrical steel sheet 10 by measuring using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry). Specifically, the grain-oriented electrical steel sheet 10 is first cleaned with an alkaline solution to remove the tension-imparting insulating coating 15, and then the glass coating 13 is removed by pickling, after which the amount is measured using ICP-AES. At this time, C and S can be measured using the combustion-infrared absorption method, N can be measured using the inert gas fusion-thermal conductivity method, and O can be measured using the inert gas fusion-non-dispersive infrared absorption method.
  • ICP-AES Inductively Coupled Plasma-Atomic Emission Spectrometry
  • the tension-imparting insulating coating can be removed by immersing the grain-oriented electrical steel sheet having the coating in a high-temperature alkaline solution. Specifically, the grain-oriented electrical steel sheet having the coating is immersed in an aqueous sodium hydroxide solution (NaOH: 30-50 mass % + H 2 O: 50-70 mass %) at 80-90°C for 5-10 minutes, and then rinsed with water and dried. This makes it possible to remove the tension-imparting insulating coating from the grain-oriented electrical steel sheet.
  • the time for immersion in the aqueous sodium hydroxide solution can be appropriately changed depending on the thickness of the tension-imparting insulating coating.
  • the glass coating can be removed by immersing the grain-oriented electrical steel sheet from which the tension-applying insulating coating has been removed in hydrochloric acid (concentration 30-40%) at 80-90°C for 1-5 minutes, rinsing with water and drying. This allows the glass coating to be removed from the grain-oriented electrical steel sheet.
  • the steel composition of a slab can be analyzed by taking a sample from the molten steel before casting, or by removing surface oxide films and other impurities from the slab after casting.
  • the remainder of the chemical composition of the steel billet and base steel sheet 11 according to this embodiment is basically Fe and impurities.
  • impurities are elements that are present in the steel billet and base steel sheet 11 regardless of the intention of their addition. In other words, they refer to elements that are mixed in from raw materials such as ore, scrap, or the manufacturing environment when the base steel sheet is industrially manufactured, and are permissible to be contained in amounts that do not adversely affect the function of the grain-oriented electrical steel sheet according to this embodiment.
  • the base steel sheet 11 of this embodiment has a secondary recrystallization texture accumulated in the ⁇ 110 ⁇ 001> orientation (Goss orientation).
  • Goss orientation a secondary recrystallization texture accumulated in the ⁇ 110 ⁇ 001> orientation
  • the average dispersion angle from the ideal Goss orientation with the rolling surface normal direction ND as the rotation axis is defined as ⁇ (°)
  • the average dispersion angle from the ideal Goss orientation with the rolling transverse direction TD as the rotation axis is defined as ⁇ (°)
  • the average dispersion angle from the ideal Goss orientation with the rolling direction RD as the rotation axis is defined as ⁇ (°)
  • the ⁇ , ⁇ , and ⁇ satisfy the following formula (1).
  • the ⁇ preferably satisfies the following formula (2).
  • the crystal orientation is specified without making a strict distinction between angle differences of about ⁇ 2.5°.
  • the angle range of about ⁇ 3.0° centered on the geometrically strict ⁇ 110 ⁇ 001> orientation is defined as the " ⁇ 110 ⁇ 001> orientation.”
  • the deviation between the actual crystal orientation of the grain-oriented electrical steel sheet and the ideal Goss orientation is defined using the following three angles ⁇ , ⁇ , and ⁇ (unit: °):
  • FIG. 2 shows a schematic diagram of the above-mentioned deviation angles ⁇ , ⁇ , and ⁇ .
  • the deviation angle ⁇ is the angle between the ⁇ 001> direction of the crystal projected onto the rolling surface when viewed from the rolling surface normal direction ND and the rolling direction RD.
  • the deviation angle ⁇ is the angle between the ⁇ 001> direction of the crystal projected onto the L cross section (cross section with the rolling direction TD as its normal) when viewed from the rolling direction TD (plate width direction) and the rolling direction RD.
  • the deviation angle ⁇ is the angle between the ⁇ 110> direction of the crystal projected onto the C cross section (cross section with the rolling direction RD as its normal) when viewed from the rolling direction RD and the rolling surface normal direction ND.
  • the misalignment angles ⁇ and ⁇ are known to affect magnetic properties.
  • the misalignment angle ⁇ affects magnetostriction.
  • Magnetostriction is a phenomenon in which a magnetic material changes shape when a magnetic field is applied.
  • Grain-oriented electrical steel sheets used in transformers and other components are required to have low magnetostriction because magnetostriction causes noise.
  • the crystal orientation is controlled so that the misalignment angle ⁇ is small (specifically, so that the maximum and average values of the absolute value of the misalignment angle ⁇ ,
  • Convention grain-oriented electrical steel sheets there is a limit to how much the misalignment angle ⁇ can be reduced, and further reduction is desired.
  • the secondary recrystallization texture of the base steel sheet satisfies the above formula (1), and preferably satisfies the above formula (2).
  • the deviation angle ⁇ exceeds 10.0°, the magnetic properties may deteriorate.
  • the deviation angles ⁇ and ⁇ have a greater effect on the magnetic properties than the deviation angle ⁇ . Therefore, the deviation angles ⁇ and ⁇ are made smaller than the deviation angle ⁇ .
  • the deviation angle ⁇ is set to 10.0° or less.
  • the deviation angle ⁇ may exceed 2.5°.
  • the lower limit of the deviation angle ⁇ is set to 4.0° or more. Furthermore, by controlling the deviation angles ⁇ and ⁇ to be less than 4.0°, the magnetic flux density in the rolling direction is improved, and good magnetic properties are obtained. From the viewpoint of improving the magnetic properties, the deviation angles ⁇ and ⁇ are preferably less than 3.5°, and more preferably less than 3.0°. However, when the deviation angle ⁇ is controlled to be 2.5° or less, the deviation angle ⁇ becomes 2.5° or more.
  • the shift angle ⁇ is 2.5° or more, there is a risk that the noise characteristics will deteriorate. Therefore, the lower limit of the shift angle ⁇ is set to be more than 2.5°, and the upper limit of the shift angle ⁇ is set to be less than 2.5°. From the above, from the viewpoint of achieving both magnetic properties and noise properties, it is effective in this embodiment for the shift angles ⁇ , ⁇ , and ⁇ to satisfy the following relationship.
  • the deviation angle ⁇ is 2.0° or less, and more preferably 1.8° or less.
  • the deviation angle ⁇ may be 0°.
  • the crystal orientation of grain-oriented electrical steel sheets can be experimentally obtained using, for example, a Laue diffractometer (RIGAKU RASCO-L II V).
  • a Laue diffractometer RIGAKU RASCO-L II V
  • a grain-oriented electrical steel sheet measuring 60 mm in width and 300 mm in length is irradiated with X-rays at intervals of 5 mm in the length direction and 5 mm in the width direction to obtain Laue diffraction spots.
  • the obtained Laue diffraction spots are then fitted using analysis software on a PC to obtain the Euler angles ⁇ 1, ⁇ , and ⁇ 2.
  • Fig. 3 is a flow chart showing an example of the flow of the manufacturing method of the grain-oriented electrical steel sheet according to the present embodiment.
  • the method for producing the grain-oriented electrical steel sheet according to this embodiment is as follows: (I) a heating step of heating a steel billet having a predetermined chemical composition; (II) a hot rolling step (step S101) of hot rolling the steel slab after the heating step to obtain a hot-rolled steel sheet; (III) A hot-rolled sheet annealing process (step S103) of annealing the hot-rolled steel sheet to obtain a hot-rolled annealed steel sheet; (IV) a cold rolling process (step S105) in which the hot-rolled annealed steel sheet is cold-rolled to obtain a cold-rolled steel sheet; (V) a decarburization annealing step (step S107) of subjecting the cold-rolled steel sheet to decarburization annealing to obtain a decarburization annealed steel sheet; (VI) a finish annealing step (step S109) of applying an annealing separator to the decarburized annealed steel sheet and then performing finish annealing to
  • Heating process In the heating step, a steel slab or other steel piece having the above-mentioned chemical composition is heated prior to hot rolling.
  • the heating temperature of the steel slab is not particularly limited, but is preferably within the range of 1100 to 1450°C.
  • the heating temperature is more preferably 1300 to 1400°C.
  • step S101 the steel slab after the heating step is hot rolled to obtain a hot rolled steel sheet.
  • the hot rolling conditions are not particularly limited and may be appropriately set based on the desired characteristics.
  • the thickness of the hot rolled steel sheet processed by hot rolling is preferably within a range of, for example, 2.0 mm to 3.0 mm.
  • the hot-rolled steel sheet annealing process is a process in which the hot-rolled steel sheet manufactured through the hot rolling process is annealed to produce a hot-rolled annealed steel sheet. By carrying out such annealing treatment, recrystallization occurs in the steel sheet structure, making it possible to realize good magnetic properties.
  • the hot-rolled steel sheet manufactured through the hot rolling process is annealed according to a known method.
  • the means for heating the hot-rolled steel sheet during annealing is not particularly limited, and any known heating method can be adopted.
  • the annealing conditions are also not particularly limited, but for example, the hot-rolled steel sheet can be annealed in a temperature range of 900 to 1200°C for 10 seconds to 5 minutes.
  • the hot rolled annealed steel sheet is subjected to cold rolling including at least one pass to obtain a cold rolled steel sheet.
  • the cold rolling does not have to include one or more intermediate annealing between each rolling pass.
  • the cold rolling may be interrupted and at least one or more intermediate annealing may be performed, so that multiple cold rolling steps including intermediate annealing are performed.
  • intermediate annealing When intermediate annealing is performed, it is preferable to hold the material at a temperature of 1000 to 1200°C for 5 to 180 seconds. There are no particular limitations on the annealing atmosphere. Taking manufacturing costs into consideration, it is preferable to perform intermediate annealing three times or less.
  • the surface of the hot-rolled steel sheet may be pickled under known conditions before rolling down.
  • the cold rolling conditions are not limited, but for example, the final rolling reduction can be in the range of 80% to 95%. If the final rolling reduction is less than 80%, it is highly likely that Goss nuclei having a high concentration of ⁇ 110 ⁇ 001> orientation in the rolling direction cannot be obtained, which is not preferable. On the other hand, if the final reduction exceeds 95%, it is undesirable because the secondary recrystallization is likely to become unstable in the subsequent finish annealing step. By setting the final reduction within the above range, Goss nuclei having a high concentration of ⁇ 110 ⁇ 001> orientation in the rolling direction can be obtained, and the instability of the secondary recrystallization can be suppressed.
  • the final reduction is the cumulative reduction of cold rolling, and if intermediate annealing is performed, it is the cumulative reduction of cold rolling after final intermediate annealing.
  • the thickness of the cold-rolled steel sheet is usually different from the thickness of the grain-oriented electrical steel sheet that is finally manufactured (product thickness including the thickness of the tension-imparting insulating coating).
  • product thickness of grain-oriented electrical steel sheet is as mentioned above.
  • the decarburization annealing process (step S107) is a process in which the cold-rolled steel sheet is subjected to decarburization annealing to obtain a decarburization annealed steel sheet, and in this embodiment, this is an important process for appropriately controlling both the texture and the inhibitors and reducing the average dispersion angle ⁇ .
  • the decarburization annealing process the cold-rolled steel sheet is subjected to primary recrystallization, and C (carbon), which adversely affects magnetic properties, is removed from the steel sheet.
  • the annealing process is performed in accordance with predetermined heat treatment conditions in the decarburization annealing process, so that the secondary recrystallized structure can be precisely controlled in the subsequent finish annealing process.
  • the decarburization annealing process according to this embodiment includes two steps, a heating step (step S131) and a soaking step (step S133), in order to obtain the desired secondary recrystallization structure.
  • the heating process is a process in which the cold-rolled steel sheet obtained in the cold rolling process is heated at a predetermined heating rate from room temperature to a temperature (maximum heating temperature) T1 (°C) in the range of 850°C to 950°C.
  • the soaking process is a process in which the cold-rolled steel sheet that has been heated at a predetermined heating rate is cooled to a predetermined temperature and annealed by holding it in a predetermined temperature range for a predetermined time.
  • the temperature increasing step according to this embodiment is an important step for precisely controlling the texture of the secondary recrystallized grains.
  • the reduction ratio (cold rolling ratio) in cold rolling is increased in order to reduce the plate thickness, but as the cold rolling ratio increases, the Goss orientation decreases and the secondary recrystallization becomes unstable.
  • the average heating rate in the temperature range of 550 to 800 ° C. is set to 400 ° C. / sec or more to increase the Goss orientation.
  • the temperature range of 550 to 800 ° C. affects the behavior of recrystallization, that is, transition.
  • the heating step recrystallization is completed at the maximum temperature reached after recovery of the structure. It is this recovery and recrystallization that have the greatest effect on the finishing annealing step (secondary recrystallization annealing step), which is the subsequent step, and in this embodiment, by setting the average heating rate in the temperature range of 550 to 800 ° C. to 400 ° C. / sec or more, it is possible to increase the number of Goss orientation nuclei having a geometrically strict ⁇ 110 ⁇ ⁇ 001>. On the other hand, if the average heating rate in this temperature range is less than 400° C./sec, it is not possible to sufficiently increase the number of Goss-oriented nuclei having a geometrically strict ⁇ 110 ⁇ 001> orientation.
  • the average heating rate in the temperature range of 550 to 800° C. is set to 3000° C./sec or less.
  • the temperature range for controlling the average heating rate is set to 550 to 800°C because this temperature range is important for enrichment and recovery of the Goss orientation.
  • This temperature range was found by the inventors by investigating the effect of the residence time at each temperature on the frequency of the Goss orientation and its recovery. That is, the inventors investigated the effect of residence time at each temperature on the frequency and recovery of the Goss orientation, and found that residence in the temperature range of 550 to 800°C reduces the frequency of the Goss orientation in the primary recrystallization texture. In other words, the frequency of the Goss orientation can be increased by increasing the heating rate in the temperature range of 550 to 800°C. If the frequency of the Goss orientation can be increased, the probability of coarsening of the Goss orientation can be increased in the final annealing process, which in turn leads to improved magnetic properties.
  • the SiO 2 formed on the steel sheet surface layer can be made thicker and denser.
  • the relationship between the SiO2 generation form and secondary recrystallization stabilization will be explained below.
  • the ratio of surface area is large, so the decomposition rate of the inhibitor is fast, and the secondary recrystallization becomes unstable.
  • the decomposition of the inhibitor is triggered by the interaction between the primary coating Mg 2 SiO 4 and AlN.
  • it is effective to reduce the formation rate of the primary coating, that is, to increase the formation temperature of the primary coating.
  • the formation rate of the primary coating is affected by the amount of SiO 2 present in the decarburized annealed steel sheet.
  • the inventors have found that the increase in the formation temperature of the primary coating can be achieved by thickening and densifying the SiO2 formed in the temperature-raising step of the decarburization annealing step.
  • the mechanism by which the formation temperature of the primary coating can be increased by thickening and densifying the SiO2 is unclear, it is believed that this is because the thickened and densified SiO2 reduces the mobility of Mg ions in the SiO2 .
  • the form of SiO 2 formed in the temperature-raising process is roughly divided into an "external oxide film” formed on the surface of the steel sheet and an “internal oxide film” formed in the surface layer of the steel sheet, and the "internal oxide film” is further divided into a "spherical oxide” and a “lamellar oxide film”.
  • the present inventors have focused on the "external oxide film” among them, and have found that by forming a thick and dense external oxide film in the temperature-raising process, the formation rate of the primary coating can be reduced (i.e., the formation temperature of the primary coating can be increased) in the subsequent finish annealing process, and the inhibitor can be stabilized (decomposition rate can be reduced).
  • the cold-rolled steel sheet is heated to a temperature (maximum heating temperature) T1 (°C) in the range of 850°C to 950°C.
  • the maximum heating temperature T1 is an effective factor in suppressing internal oxidation in the subsequent soaking process.
  • the maximum heating temperature T1 is set to 850°C or higher. This makes it possible to suppress internal oxidation in the soaking process (suppressing the formation of spherical oxides and lamellar oxide films).
  • the maximum heating temperature T1 is 870°C or higher, more preferably 900°C or higher.
  • excessively increasing the maximum heating temperature T1 leads to excessive strain on the equipment, so the maximum heating temperature T1 is set to 950°C or lower.
  • the outer oxide film of SiO 2 formed on the steel sheet surface can be formed thick and dense.
  • the average temperature rise rate in the temperature range from 800 to the maximum heating temperature T1 (°C) is less than 100°C/sec, the thickness of the outer oxide film of SiO 2 becomes insufficient, and oxide films other than SiO 2 (e.g., Fe 2 SiO 4 , etc.) are allowed. Oxide films other than SiO 2 may promote the decomposition of the inhibitor during the final annealing process.
  • the average temperature rise rate in the temperature range from 800 to the maximum heating temperature T1 (°C) is set to 100°C/sec or more, preferably 200°C/sec or more, and more preferably 400°C/sec or more.
  • the control range of the average heating rate in the heating process is 550 to the maximum heating temperature T1 (°C).
  • the average heating rate in the temperature range from 550 to the maximum heating temperature T1 (°C) to 100°C/sec or more.
  • the preferable temperature range to be controlled is 600 to the maximum heating temperature T1 (°C), and more preferably 650 to the maximum heating temperature T1 (°C).
  • the upper limit of the average heating rate in the temperature range from 800 to the maximum heating temperature T1 (°C) does not need to be limited from the viewpoint of characteristics, but since special equipment is required to obtain an average heating rate exceeding 1500°C/sec, the average heating rate is set to 1500°C/sec or less.
  • the dew point of the atmosphere during the temperature rise from 800°C to the maximum heating temperature T1 (°C) is set to 0°C or less.
  • the dew point in the temperature rise process also affects the formation of oxide films other than SiO2 .
  • the dew point of the atmosphere in the temperature range from 800 to the maximum heating temperature T1 (°C) is set to 0°C or less, preferably -5°C or less, and more preferably -10°C or less.
  • setting the dew point of the atmosphere to 0°C or less in the temperature range from room temperature to less than 800°C does not impair the effect of the present invention.
  • a soaking step is carried out. If carbon remains in the steel sheet, the core loss properties will deteriorate over time (known as magnetic aging). Therefore, the atmosphere during decarburization annealing is usually set to a relatively high oxygen potential in order to reduce the amount of carbon. However, during the annealing process, if the oxygen potential of the atmosphere is high, the amount of SiO2 produced will increase, and the rate of primary coating formation will increase. Therefore, in the soaking step, the annealing atmosphere is set at a low oxygen potential, which reduces the rate at which the primary coating is formed.
  • the cold-rolled steel sheet is preferably held for 100 to 300 seconds in an atmosphere with a temperature of 780 to 860° C. and an oxygen potential (PH 2 O/PH 2 ) of 0.20 to 0.60.
  • the sheet is heated to a temperature exceeding the holding temperature in the soaking step in the temperature increase step, and therefore is cooled to a predetermined soaking holding temperature by air cooling or natural cooling when transitioning to the soaking step, but this cooling does not impair the effect shown in this embodiment.
  • the holding temperature in the soaking step is less than 780°C, decarburization will be insufficient due to the diffusion rate limiting factor. If decarburization is insufficient, carbon will remain in the steel sheet, causing iron loss deterioration. Alternatively, secondary recrystallization itself will not occur due to a phase change.
  • the holding temperature exceeds 860° C., the interface rate-determining factor also restricts the decarburization, resulting in poor decarburization, because a coating oxide film that is harmful to decarburization is formed.
  • the oxygen potential in the soaking process is less than 0.20, decarburization is poor. Decarburization is a chemical reaction between carbon in the steel sheet and oxygen in the annealing atmosphere.
  • a low oxygen potential is synonymous with a low oxygen partial pressure, and means a situation in which the decarburization reaction is difficult to occur.
  • the oxygen potential during the soaking step exceeds 0.60, decarburization is also poor, because a coating oxide film that inhibits decarburization is formed.
  • the ambient dew point temperature may be set to 30 to 80°C using a mixture of nitrogen and hydrogen gas or nitrogen gas.
  • a nitriding treatment may be carried out between the decarburization annealing step and the finish annealing step described below.
  • the cold-rolled steel sheet after the decarburization annealing process is maintained at about 700 to 850 ° C. in a nitriding atmosphere (an atmosphere containing hydrogen, nitrogen, and ammonia or other gases having nitriding ability).
  • a nitriding atmosphere an atmosphere containing hydrogen, nitrogen, and ammonia or other gases having nitriding ability.
  • the N content of the cold-rolled steel sheet after the nitriding process is less than 40 ppm, AlN does not precipitate sufficiently in the cold-rolled steel sheet, and AlN may not function as an inhibitor. For this reason, when AlN is used as an inhibitor, it is preferable that the N content of the cold-rolled steel sheet is 40 ppm or more. On the other hand, when the N content of the cold-rolled steel sheet exceeds 1000 ppm, excess AlN remains in the steel sheet even after the secondary recrystallization is completed in the finish annealing. Such AlN causes iron loss deterioration. For this reason, the N content of the steel sheet is preferably 1000 ppm or less.
  • step S109 an annealing separator is applied to the decarburized annealed steel sheet (after the decarburization annealing step or the nitriding treatment step), and then finish annealing is performed to obtain a finish annealed steel sheet.
  • the finish annealing conditions are not limited, but may be, for example, performed under conditions in which the temperature is raised to 1150 to 1250° C. in an atmospheric gas containing hydrogen and nitrogen, and annealing (holding) is performed in that temperature range for 10 to 60 hours.
  • the final annealing is performed for a long time while the steel sheet is wound in a coil shape. Therefore, prior to the final annealing, an annealing separator is applied to the cold-rolled steel sheet and dried in order to prevent the inside and outside of the coil from seizing.
  • the annealing separator to be applied is an annealing separator mainly composed of MgO.
  • MgO a glass coating can be formed on the surface of the base steel sheet. If MgO is not the main component, the primary coating (glass coating) is not formed. This is because the primary coating is an Mg 2 SiO 4 or MgAl 2 O 4 compound, and Mg required for the formation reaction is insufficient.
  • the annealing separator applied to the decarburization annealed steel sheet preferably contains one or more elements selected from Ti, Sb, Sr and Cl in an amount of 0.10 to 10.00% in total, relative to the weight of MgO.
  • the total content of Ti, Sb, Sr, and Cl is preferably 0.10 to 10.00% by weight. If the total content of Ti, Sb, Sr, and Cl is less than 0.10% by weight of MgO, the effect of improving the magnetic properties may not be sufficient. On the other hand, if the total content of Ti, Sb, Sr, and Cl exceeds 10.00%, a sufficient amount of the primary coating is not formed, and the coating tension effective for improving the magnetic properties cannot be secured, which may result in inferior core loss.
  • the forms (i.e., means of addition) of Ti, Sb, Sr and Cl in the annealing separator may be as compounds or as simple substances. For example, when Ti is contained in the annealing separator, it may be contained as Ti simple substance or as Ti oxide (e.g., TiO 2 ).
  • an insulating coating (tensioned insulating coating) is formed on the surface (one side or both sides) of the finish annealed steel sheet.
  • the conditions for forming the insulating coating are not particularly limited, and a known insulating coating treatment liquid may be used, and the treatment liquid may be applied and dried by a known method.
  • the surface of the steel sheet on which the insulating coating is formed may be a surface that has been subjected to any pretreatment, such as degreasing with an alkali or pickling with hydrochloric acid, sulfuric acid, phosphoric acid, etc., before the treatment liquid is applied, or it may be a surface that has not been subjected to any of these pretreatments and is left as it is after finish annealing.
  • any pretreatment such as degreasing with an alkali or pickling with hydrochloric acid, sulfuric acid, phosphoric acid, etc.
  • the insulating coating formed on the surface of the steel sheet is not particularly limited as long as it is used as an insulating coating for directional electrical steel sheets, and known insulating coatings can be used.
  • insulating coatings include coatings mainly composed of phosphate and colloidal silica.
  • composite insulating coatings include inorganic substances that also contain organic substances.
  • composite insulating coatings are insulating coatings that are mainly composed of at least one of inorganic substances such as metal chromate salts, metal phosphate salts, colloidal silica, Zr compounds, and Ti compounds, and in which fine organic resin particles are dispersed.
  • insulating coatings that use metal phosphate salts, Zr or Ti coupling agents, or carbonates or ammonium salts of these as starting materials may be used.
  • the method for producing a grain-oriented electrical steel sheet according to this embodiment may include a magnetic domain refining step after the insulating coating forming step.
  • a plurality of linear strains thermal strains caused by rapid heating by energy beam irradiation and subsequent rapid cooling
  • energy beams such as laser beams or electron beams
  • the intervals at which the plurality of linear strains are formed are preferably 3.0 to 9.0 mm in the rolling direction.
  • the energy beam include a laser beam and an electron beam.
  • the laser beam may be a continuous wave laser or a pulsed laser.
  • Examples of the type of laser beam include a fiber laser, a YAG laser, or a CO2 laser.
  • the electron beam may be a continuous beam or an intermittent beam.
  • the surface scale was removed from the hot-rolled steel sheet after hot rolling and annealing (hot-rolled annealed steel sheet) by pickling or the like, and then cold rolling including multiple passes without intermediate annealing was performed to produce a cold-rolled steel sheet having a sheet thickness of 0.16 to 0.23 mm.
  • the obtained cold-rolled steel sheet was subjected to decarburization annealing under the conditions shown in Table 3.
  • the holding time in the soaking process was 120 seconds.
  • Test Nos. 1, 2, 9, 10, 14, and 15 were further subjected to a nitriding treatment in which the nitrogen content was increased to 200 ppm.
  • the decarburized annealed steel sheet was subjected to a final annealing process.
  • an annealing separator mainly composed of MgO and containing the elements listed in Table 3 was applied to the surface of the cold-rolled steel sheet by applying a water slurry.
  • the components contained in the annealing separator listed in Table 3 indicate the weight fractions of the individual elements.
  • the decarburized annealed steel sheet coated with the annealing separator was held at 1200°C for 20 hours to produce a steel sheet (finish annealed steel sheet) with a primary coating (glass coating) on the base steel sheet.
  • an insulating coating was formed on this steel sheet. Specifically, an insulating coating forming liquid mainly composed of colloidal silica and phosphate was applied to the surface of the steel sheet (more specifically, the surface of the glass coating, which is the primary coating), and heat-treated (baked). This resulted in a grain-oriented electrical steel sheet comprising a base steel sheet, a glass coating formed on the base steel sheet, and an insulating coating formed on the glass coating.
  • the chemical composition of the base steel sheet of the obtained grain-oriented electrical steel sheet is shown in Table 2. Note that the notation "-" in the chemical composition in Table 2 means that the content of the corresponding element is 0% in significant figures (numbers up to the lowest digit) specified in the embodiment.
  • the magnetic properties (iron loss and magnetic flux density) of the obtained grain-oriented electrical steel sheets were evaluated as follows. The results are shown in Table 4.
  • the samples after the laser irradiation were subjected to a magnetic evaluation using a single sheet magnetic test (SST) device to measure the core loss (W 17/50 ).
  • SST single sheet magnetic test
  • a magnetic field of 800 A/m was also applied to the samples to measure the magnetic flux density B 8 (T).
  • the core loss (W 17/50 ) was evaluated according to the following criteria, with ratings A to C being judged to be excellent (low core loss) and rating D being judged to be poor.
  • Grade A 0.70 or more but less than 0.75 Grade B 0.75 or more but less than 0.80: Grade C 0.80 or more: Grade D
  • the magnetostriction of the sample having a width of 60 mm and a length of 300 mm that had been subjected to the above-mentioned magnetic domain control was measured by an AC magnetostriction measurement method using a magnetostriction measurement device that was equipped with a laser Doppler vibrometer, an excitation coil, an excitation power supply, a magnetic flux detection coil, an amplifier, and an oscilloscope.
  • an AC magnetic field was applied to the sample so that the maximum magnetic flux density in the rolling direction was 1.7 T.
  • the change in length of the sample due to expansion and contraction of the magnetic domains was measured with a laser Doppler vibrometer to obtain a magnetostriction signal.
  • the obtained magnetostriction signal was subjected to Fourier analysis to determine the amplitude Cn of each frequency component fn (n is a natural number equal to or greater than 1) of the magnetostriction signal.
  • the A correction coefficient ⁇ n for each frequency component fn was used to determine the magnetostriction velocity level LVA (dB) given by the following formula.
  • the noise characteristics were evaluated in accordance with the following criteria. If the magnetostriction rate level was 60.0 dBA or less, it was judged to have "excellent noise characteristics” (grade C). If it was 57.5 dBA or less, it was judged to be even better (grade B), and if it was 55.0 dBA or less, it was judged to be particularly excellent (grade A). If the magnetostriction rate level was more than 60.0 dBA, it was judged to have "inadequate noise characteristics (grade D)".

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