WO2023068236A1 - Tôle d'acier électromagnétique à grains orientés et son procédé de production - Google Patents

Tôle d'acier électromagnétique à grains orientés et son procédé de production Download PDF

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Publication number
WO2023068236A1
WO2023068236A1 PCT/JP2022/038635 JP2022038635W WO2023068236A1 WO 2023068236 A1 WO2023068236 A1 WO 2023068236A1 JP 2022038635 W JP2022038635 W JP 2022038635W WO 2023068236 A1 WO2023068236 A1 WO 2023068236A1
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mass
less
annealing
basis weight
steel sheet
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PCT/JP2022/038635
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English (en)
Japanese (ja)
Inventor
誠 渡邉
拓弥 山田
敬 寺島
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Ｊｆｅスチール株式会社
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Priority to JP2023513545A priority Critical patent/JPWO2023068236A1/ja
Publication of WO2023068236A1 publication Critical patent/WO2023068236A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present invention is a grain-oriented electrical steel sheet mainly used for iron cores of transformers, electric motors, generators, etc., especially iron cores of small generators and small electric motors, or winding cores and EI cores.
  • the present invention relates to a grain-oriented electrical steel sheet in which twinning is unlikely to occur even when subjected to shearing or the like, and a method for producing the same.
  • Grain-oriented and non-oriented electrical steel sheets are widely used as iron core materials for various transformers, electric motors, generators, etc.
  • grain-oriented electrical steel sheets are highly concentrated in the ⁇ 110 ⁇ 001> orientation known as the Goss orientation, so they have high magnetic flux density and low iron loss. It is characterized by having good iron loss characteristics, which directly leads to the reduction of energy loss.
  • grain-oriented electrical steel sheets When such grain-oriented electrical steel sheets are used to manufacture iron cores for small generators and small electric motors, or EI cores, etc., they are subjected to a leveler process for correcting the shape of the coil, followed by punching or shearing. often do However, during the leveler treatment, punching, and shearing, the steel sheet may undergo twinning deformation, resulting in cracking, chipping, or warping, which may cause manufacturing troubles. Also, when manufacturing a wound core, twinning may occur when a steel sheet is wound and deformed into a core shape, degrading the magnetic properties.
  • Patent Document 1 by reducing S and N in the raw material components and adding 0.5 to 5.0 mass% of the SO 3 component mass of the SO 3 compound to the annealing separator, twinning is achieved. Techniques for suppressing the generation have been proposed.
  • Patent Document 2 describes a technique for forming a forsterite coating with excellent coating properties by including a Ti compound in an annealing separator, wherein the Ti concentration of the steel sheet including the forsterite coating is 1 with respect to the N concentration. Techniques have been proposed to prevent cracking during shearing and bending by reducing N in the steel to a range of 0.0 to 2.0 times.
  • Patent Document 3 discloses a technique for reducing the number of origins of twinning by refining the secondary recrystallized grain size in the direction perpendicular to rolling (C direction) and reducing the unevenness of the film/base iron interface. It is
  • Refining the secondary grain size in the direction perpendicular to rolling, as described in Patent Document 3, is effective in reducing twins. , the secondary recrystallized grains are coarsened, so there is room for improvement in that strict control is required.
  • the present invention has been made in view of the above-mentioned circumstances of the prior art.
  • a grain-oriented electrical steel sheet that does not suffer from cracking or chipping due to twinning deformation even in applications that undergo strong processing, such as iron cores and winding cores of small generators, and that does not deteriorate in magnetic properties. to propose.
  • the inventors have developed a grain-oriented electrical steel sheet having good coating properties, which has a Ti-containing forsterite coating as a base coating formed by applying an annealing separator containing a Ti compound. Extensive experiments were conducted, and measures to reduce the twinning rate compared to the conventional technology were examined. As a result, it was found that the oxygen basis weight of the undercoat and the amount of Ti contained in the undercoat have a great effect on the occurrence of twins. The inventors have newly found that it is effective to increase the oxygen basis weight and limit the amount of Ti in the undercoat, and have developed the present invention. That is, the gist and configuration of the present invention are as follows.
  • a steel slab having a chemical composition containing 0.005 to 0.03 mass% and the balance being Fe and unavoidable impurities is hot-rolled to form a hot-rolled sheet, and the hot-rolled sheet is subjected to one or intermediate annealing.
  • a cold-rolled sheet is obtained by sandwiching and cold-rolling two or more times, and the cold-rolled sheet is subjected to primary recrystallization annealing, then an annealing separator is applied, and then finish annealing is performed to obtain a finish-annealed sheet.
  • a method for producing a grain-oriented electrical steel sheet comprising applying a coating liquid to an annealed sheet and performing flattening annealing to obtain a grain-oriented electrical steel sheet,
  • the oxygen basis weight on the surface of the steel sheet after the primary recrystallization annealing is 1.5 g/m 2 or more and 2.1 g/m 2 or less, and as the annealing separator, TiO 2 is 0.6 per 100 parts by mass of MgO.
  • a method for producing a grain-oriented electrical steel sheet characterized by using an annealing separator containing up to 2.7 parts by mass, and setting the rate of temperature increase between 700 to 950°C in the final annealing to 15°C/h or more. .
  • the chemical composition of the steel slab further includes Al: 0.003 to 0.015 mass%, N: 0.001 to 0.007 mass%, Cu: 0.01 to 0.14 mass%, Ni: 0.01 to 0. .3 mass%, Cr: 0.01 to 0.06 mass%, Sb: 0.004 to 0.04 mass%, Sn: 0.005 to 0.04 mass%, Mo: 0.01 to 0.1 mass%, B: 0.001 to 0.01mass%, P: 0.005 to 0.06mass%, Nb: 0.002 to 0.02mass%, Bi: 0.001 to 0.01mass%, Ge: 0.001 to 0.01mass% 05 mass%, As: 0.005 to 0.05 mass%, Te: 0.005 to 0.02 mass%, Ti: 0.005 to 0.04 mass% and V: 0.005 to 0.03 mass% 3.
  • the present invention it is possible to provide a grain-oriented electrical steel sheet that is less likely to undergo twinning deformation and has less deterioration in magnetic properties even when used for applications that require strong working. Therefore, by using the grain-oriented electrical steel sheet of the present invention, it is possible not only to reduce troubles such as cracks and chips when processing iron cores and wound cores of small generators, but also to reduce energy loss in generators, transformers, etc. enables the production of
  • the oxygen basis weight of the decarburized annealed sheet after primary recrystallization annealing (hereinafter also referred to as the oxygen basis weight after decarburization annealing), the oxygen basis weight and the Ti basis weight of the undercoat Table 1 shows the measurement results of , and the investigation results of the magnetic flux density and twinning rate in the steel sheet.
  • the above oxygen basis weight can be measured by a melting-infrared absorption method.
  • the Ti basis weight can be measured by emission spectroscopy.
  • the magnetic flux density is the magnetic flux density when excited at 800 A / m: B 8 (T) according to JIS It was measured according to the method specified in C2550.
  • the oxygen basis weight after decarburization annealing should be increased, and the amount of TiO 2 in the annealing separator should be increased. Both increasing the amount contributes.
  • the oxygen basis weight after decarburization annealing was increased too much, the oxygen basis weight of the undercoat decreased rapidly.
  • the strength of the coating is increased by introducing S into the coating as described in Patent Document 1 above, or by adjusting the ratio of Ti and N as described in Patent Document 2. It is known that increasing In contrast, the above findings suggest that factors other than film strength are involved. That is, the present inventors considered that it is important not to directly transmit the coating tension due to the overcoat to the steel substrate. In other words, the top coat applies stress in the tensile direction to the steel sheet, and under this condition, twinning occurs when deformation stress is further applied. Conversely, if the film stress is not applied, twins are unlikely to occur even with some deformation stress.
  • the oxygen basis weight of the undercoating is increased by a certain amount or more, the stress of the overcoating coating in the upper layer is relaxed in the undercoating, and the stress applied to the base steel is reduced. Further, as the Ti content in the undercoat increases, the tension in the undercoat itself increases, so twinning is more likely to occur.
  • the oxygen basis weight of the undercoating generally correlates with the oxygen basis weight of the surface of the steel sheet after decarburization annealing, increasing this increases the oxygen basis weight of the undercoating.
  • the oxygen basis weight after decarburization annealing is too high, the amount of the undercoat formed will be too large, and the undercoat will partially peel off, thereby decreasing the oxygen basis weight of the undercoat. Therefore, there is an appropriate range for the oxygen basis weight after decarburization annealing.
  • the Ti source is TiO 2 in the annealing separator
  • the Ti basis weight is almost correlated with the amount of TiO 2 added.
  • the basis weight of oxygen after decarburization annealing also has an effect. This is because when the oxygen basis weight after decarburization annealing is high, oxides present in the subscale surface layer, such as Fe 2 SiO 4 , and TiO 2 undergo a substitution reaction to form FeTiO 3 . It is considered that the amount of Ti in the coating increases because Ti easily penetrates into the coating.
  • both the oxygen basis weight after decarburization annealing and the amount of TiO2 added in the annealing separator affect both the oxygen basis weight and the Ti basis weight of the undercoat.
  • the oxygen basis weight and the Ti basis weight of the undercoat can be kept within appropriate ranges, and the twinning rate can be reduced.
  • the undercoating has an oxygen basis weight of 3.8 g/m 2 or more and a Ti basis weight of 0.06 g/m 2 or less. This is based on the above-described new knowledge that strain due to tension in the overcoat promotes twinning, and that if the stress caused by the overcoat is relieved by the undercoat, the occurrence of twins can be suppressed. That is, when the oxygen basis weight of the undercoat is less than 3.8 g/m 2 , the ability of the undercoat to relax the tension of the coating decreases, resulting in an increase in twinning rate.
  • the oxygen basis weight should be 3.8 g/m 2 or more and the Ti basis weight should be 0.06 g/m 2 or less.
  • the oxygen basis weight of the undercoat is preferably 5.0 g/m 2 or less. From the same point of view, it is preferable that the Ti basis weight in the undercoating is 0.01 g/m 2 or more.
  • the grain-oriented electrical steel sheet targeted by the present invention preferably has a magnetic flux density of 1.88 T or less at B8 .
  • the reason why it is desirable to lower the magnetic flux density is that when the magnetic flux density is high, the secondary recrystallized grain size usually becomes large, the grain boundary density decreases, and twin crystals are likely to develop. If the secondary recrystallized grain size is made finer by setting the magnetic flux density to a lower value, it is possible to prevent the strain imparted during working from being locally concentrated, making it easier to prevent twinning deformation. Therefore, the present invention cannot be applied to, for example, a technique in which a coil is annealed under a temperature gradient to elongate secondary recrystallized grains. Also, the technique of growing secondary recrystallized grains by holding in the secondary recrystallization temperature range during final annealing is not suitable for the present invention.
  • C 0.001 to 0.10 mass%
  • C is a component necessary for generating Goss-oriented crystal grains, and should be contained in an amount of 0.001 mass% or more in order to exhibit such an effect.
  • addition exceeding 0.10 mass% makes it difficult to decarburize to a level that does not cause magnetic aging in the subsequent decarburization annealing. Therefore, the C content should be in the range of 0.001 to 0.10 mass%.
  • the content of C is preferably 0.015 mass% or more, and preferably 0.08 mass% or less.
  • Al, N, Cu, Ni, Cr, Sb, Sn, Mo, B, P, Nb and Bi segregate on the grain boundaries and on the surface of the steel sheet and act as auxiliary inhibitors to improve the magnetic properties.
  • the grain-oriented electrical steel sheet of the present invention is produced by melting steel having the chemical composition described above by a conventionally known refining process, and using a continuous casting method or an ingot casting-slabbing rolling method or the like to form a steel material (steel slab). After that, the steel material is hot-rolled to obtain a hot-rolled sheet, and if necessary, hot-rolled sheet annealing is performed, and cold rolling is performed once or twice or more with intermediate annealing.
  • the cold-rolled sheet shall be thick.
  • the reason why the oxygen basis weight on the surface of the steel sheet after primary recrystallization annealing is 1.5 to 2.1 g/m 2 is to set the oxygen basis weight and the Ti basis weight in the undercoating to appropriate ranges. .
  • the oxygen basis weight is less than 1.5 g/m 2 , the formation of the undercoat becomes insufficient, and when the oxygen basis weight exceeds 2.1 g/m 2 , the formation of the undercoat becomes excessive. In the end, point-like peeling occurs, and a sufficient effect cannot be obtained.
  • the annealing temperature is preferably 700 to 900° C. and the annealing time is preferably 30 to 300 seconds. If the annealing temperature is less than 700° C. or the annealing time is less than 30 seconds, the desired oxygen basis weight cannot be secured or decarburization becomes insufficient. On the other hand, if the annealing temperature exceeds 900° C. or the annealing time exceeds 300 seconds, the oxygen basis weight becomes excessive. Also, the decarburization annealing is performed in a wet hydrogen atmosphere.
  • the dew point is in the range of 45 to 60° C.
  • the H 2 concentration is a conventional method, which can be in the range of 40% to 80%.
  • the oxygen basis weight can be adjusted.
  • This PH 2 O/PH 2 is desirably in the range of 0.40 to 0.55. It is also possible to change at each stage of the heating zone and soaking zone.
  • the soaking area can be divided into two stages, a front stage and a rear stage. Both or one of the soaking temperature and the atmospheric oxidizing PH 2 O/PH 2 conditions are different between the former stage and the latter stage.
  • the temperature difference between the former stage and the latter stage shall be 20°C or more. If oxidizing, change the PH 2 O/PH 2 difference by 0.2 or more.
  • the temperature is not particularly limited, but the latter stage should be higher than the former stage.
  • PH 2 O/PH 2 is often lower in the latter stage than in the former stage, and this can be followed in the present invention.
  • the pretreatment of the primary recrystallization annealing For example, when cleaning a rolled sheet (cold-rolled sheet), electrolytic degreasing is performed with a degreasing solution (electrolytic solution) containing sodium silicate. As a result, the SiO 2 compound is electrodeposited on the surface of the steel sheet, which serves as a starting point for oxidation during decarburization annealing, and can increase the oxygen basis weight.
  • the oxygen basis weight after the primary recrystallization annealing changes depending on the material composition and the previous process, it is necessary to adjust the annealing conditions according to each process. For example, if the Si content in the steel material is as low as 3 mass% or less, the oxygen basis weight tends to decrease, so the dew point is set high. In addition, if the steel sheet surface before primary recrystallization annealing has a high oxygen basis weight of 0.1 g/m 2 or more, it is effective to set the dew point to a lower value.
  • the surface of the steel sheet is coated with an annealing separator containing MgO as a main component.
  • the annealing separating agent used is one to which TiO 2 is added.
  • the reason why TiO 2 is added here is mainly from the viewpoint of enhancing film adhesion, and this addition of TiO 2 has been conventionally performed.
  • the second feature of the present invention is that the amount of TiO 2 added is kept to a very small amount. That is, the amount of TiO 2 added to the annealing separator used in the present invention is in the range of 0.6 to 2.7 parts by mass when MgO is 100 parts by mass.
  • the amount (content) of TiO 2 added to the annealing separating agent is less than 0.6 parts by mass, the film adhesion is lowered, and the underlying pattern is generated.
  • the amount of TiO 2 added to the annealing separator is higher than 2.7 parts by mass, the amount of Ti contained in the undercoating exceeds 0.06 g/m 2 in terms of Ti basis weight, and the twinning rate increases. will do.
  • the conditions of the annealing separator other than the amount of TiO 2 added may be as known.
  • additives for the annealing separator include borates such as Li, Na, K, Mg, Ca, Sr, Sn, Sb, Cr, Fe, and Ni, sulfates, carbonates, and water. Oxides, chlorides and the like can be added singly or in combination.
  • the amount of the annealing separator applied to the surface of the steel sheet is preferably 8 to 16 g/m 2 on both sides, and the hydration amount is preferably in the range of 0.5 to 3.7 mass%.
  • the annealing separating agent is usually made into a slurry with water, coated with a roll coater, and then dried. This method can also be used in the present invention.
  • a third feature of the present invention is to specify the rate of temperature increase at this time. That is, the rate of temperature increase between 700 and 950° C. in the final annealing must be 15° C./h or more.
  • This temperature range is the temperature range in which the formation of the undercoating begins in earnest, and is also the temperature range immediately before TiO 2 in the annealing separator decomposes and Ti penetrates into the undercoating. If the rate of temperature rise in this temperature range is slow, the substitution reaction that forms FeTiO3 from Fe2SiO4 proceeds too much, Ti penetrates too much into the film, and the Ti content in the undercoat increases.
  • the rate of temperature increase between 700 and 950° C. in the final annealing should be 15° C./h or more, preferably 20° C./h or more.
  • the final annealing (retaining treatment) is generally performed at a temperature of 1150° C. or higher and 1250° C. or lower for a time of 3 hours or longer and 50 hours or shorter, and the present invention is also within this range. If the temperature is lower than 1150° C. or the time is shorter than 3 hours, purification may be insufficient and precipitates may remain, resulting in an increased twinning rate. On the other hand, if the temperature is higher than 1250° C. or the time is longer than 50 hours, the coil may buckle and the yield may decrease.
  • an insulating coating is applied and flattening annealing, which also serves as baking, is performed.
  • flattening annealing which also serves as baking
  • a steel slab having a chemical composition in which the balance is Fe and unavoidable impurities is heated at 1410 ° C. for 30 minutes, hot-rolled to a hot-rolled sheet with a thickness of 2.5 mm, and heated at 1000 ° C. for 1 minute.
  • the hot-rolled sheet was annealed. After that, it was cold-rolled to a thickness of 0.9 mm, subjected to intermediate annealing at 980° C. for 1 minute, and then cold-rolled to a final thickness of 0.35 mm.
  • primary recrystallization annealing which also serves as decarburization annealing, was performed at 850° C. for 120 seconds in an atmosphere with a PH 2 O/PH 2 ratio of 0.51.
  • the oxygen basis weight of the decarburized annealed sheet was set to 2.0 g/m 2 .
  • powder obtained by adding 2.4 parts by mass of TiO 2 and 0.1 part by mass of Li 2 SO 4 to 100 parts by mass of MgO as an annealing separator was made into a slurry, and the amount of hydration was 1.0 parts by mass. It was coated on both sides of the steel sheet at 11 g/m 2 so as to be 3 mass%.
  • the temperature was raised between 700 and 950° C. at various heating rates shown in Table 2, followed by holding treatment at 1160° C. for 5 hours for purification.
  • a hot-rolled sheet was annealed at 1000° C. for 1 minute. After that, it was cold rolled to an intermediate plate thickness of 0.8 mm, subjected to intermediate annealing at 1000° C. for 2 minutes, and further cold rolled to obtain a cold rolled plate having a final thickness of 0.27 mm.
  • a coating liquid consisting of magnesium phosphate-colloidal silica-titanium sulfate was applied, and flattening annealing was performed for both baking and shape correction of the steel sheet to obtain a product coil (grain-oriented electrical steel sheet).
  • the steel sheets thus obtained were examined for magnetic flux density B8 and twinning rate.
  • the results are shown in Table 3 together with the oxygen basis weight after primary recrystallization annealing, the oxygen basis weight in the undercoat and the Ti basis weight.
  • the oxygen basis weight after the primary recrystallization annealing, the oxygen basis weight and Ti basis weight in the undercoat, the magnetic flux density B8 and the twinning rate were measured according to the measurement method described above.

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Abstract

La présente invention concerne une tôle d'acier électromagnétique à grains orientés qui est exempte de défauts tels que la fissuration et l'écaillage dus à une déformation par maclage même si elle est appliquée à un noyau d'enroulement ou à un noyau de fer d'un petit générateur d'énergie ou semblable, étant ainsi soumise à un traitement intense, et qui est également exempte de détérioration des caractéristiques magnétiques. La présente tôle d'acier électromagnétique à grains orientés a une composition de composant qui contient 2,8 % en masse à 3,5 % en masse de Si et 0,01 % en masse à 1,0 % en masse de Mn, le reste étant constitué de Fe et d'impuretés inévitables, tout en ayant un film de revêtement de base qui est principalement composé de forstérite et contient du Ti, et un film de revêtement supérieur qui est formé sur le film de revêtement de base. Par rapport à la présente tôle d'acier électromagnétique à grains orientés, le film de revêtement de base a un poids d'oxygène par mètre carré de 3,8 g/m2 ou plus et un poids de Ti par mètre carré de 0,06 g/m2 ou moins.
PCT/JP2022/038635 2021-10-20 2022-10-17 Tôle d'acier électromagnétique à grains orientés et son procédé de production WO2023068236A1 (fr)

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61238939A (ja) * 1985-04-15 1986-10-24 Kawasaki Steel Corp 高周波特性の優れたけい素鋼薄鋼板およびその製造方法
JPH09184017A (ja) * 1996-01-08 1997-07-15 Kawasaki Steel Corp 高磁束密度一方向性けい素鋼板のフォルステライト被膜とその形成方法
JPH1060533A (ja) * 1996-08-13 1998-03-03 Kawasaki Steel Corp 磁気特性及び被膜特性に優れる方向性けい素鋼板の製造方法
WO2008047999A1 (fr) * 2006-10-18 2008-04-24 Posco Agent de separation de recuit pour tole d'acier electrique a grains orientes presentant un film de verre uniforme et d'excellentes proprietes magnetiques, et procede de fabrication associe
JP2016145419A (ja) * 2015-01-30 2016-08-12 Ｊｆｅスチール株式会社 方向性電磁鋼板とその製造方法
JP2018066062A (ja) * 2016-10-19 2018-04-26 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61238939A (ja) * 1985-04-15 1986-10-24 Kawasaki Steel Corp 高周波特性の優れたけい素鋼薄鋼板およびその製造方法
JPH09184017A (ja) * 1996-01-08 1997-07-15 Kawasaki Steel Corp 高磁束密度一方向性けい素鋼板のフォルステライト被膜とその形成方法
JPH1060533A (ja) * 1996-08-13 1998-03-03 Kawasaki Steel Corp 磁気特性及び被膜特性に優れる方向性けい素鋼板の製造方法
WO2008047999A1 (fr) * 2006-10-18 2008-04-24 Posco Agent de separation de recuit pour tole d'acier electrique a grains orientes presentant un film de verre uniforme et d'excellentes proprietes magnetiques, et procede de fabrication associe
JP2016145419A (ja) * 2015-01-30 2016-08-12 Ｊｆｅスチール株式会社 方向性電磁鋼板とその製造方法
JP2018066062A (ja) * 2016-10-19 2018-04-26 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法

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