Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C45/00—Amorphous alloys
  • C22C45/02—Amorphous alloys with iron as the major constituent
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
  • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
  • B22D11/0611—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by a single casting wheel, e.g. for casting amorphous metal strips or wires
• • 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
  • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
• • 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
  • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
• • 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
  • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
  • H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
• • 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
  • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
  • H01F1/15341—Preparation processes therefor
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
  • B22D11/16—Controlling or regulating processes or operations
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/26—Methods of annealing
• • 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
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/007—Heat treatment of ferrous alloys containing Co

Definitions

• the present invention relates to a method for producing an iron-based crystal alloy, and more particularly to a method for producing an iron-based crystal alloy that can be suitably used as a core material applied to a direct current motor.
• the above Fe-Si-B-based amorphous alloy ribbon has a lower iron loss than that of a silicon steel sheet, it has been studied to improve motor efficiency by applying the Fe-Si-B-based amorphous alloy ribbon to a rotor core and a stator core of a brushless direct current (BLDC) motor by taking advantage of this feature.
• BLDC brushless direct current
• the Fe-Si-B-based amorphous alloy ribbon is used in a high-speed rotation type BLDC motor exceeding 20,000 rpm, since high motor efficiency can be obtained as the operation range of the soft magnetic material becomes a high-frequency band around 2 kHz, it is expected that the Fe-Si-B-based amorphous alloy ribbon is applied to major appliances, such as vacuum cleaners, and electric auxiliary motors that require high-speed rotation of the motor.
• a drive motor for EV which is required to have higher efficiency than that of a motor for major appliances, cannot obtain a required output unless a saturation magnetic flux density (Bs) equivalent to that of a silicon steel sheet can be ensured. Since Bs of the Fe-Si-B-based amorphous alloy is about 1.6 T at the maximum, it is difficult to replace a silicon steel sheet having Bs of 1.7 T or more. For this reason, there has been no example in which an EV drive BLDC motor using the Fe-Si-B-based amorphous alloy has been put on the market.
• a core material of a silicon steel sheet and an anisotropic rare earth iron-boron-based sintered magnet exhibiting excellent permanent magnet characteristics are combined, and high efficiency by utilizing magnet torque has been conventionally promoted.
• a silicon steel sheet having a low magnetic permeability the excellent magnetic characteristics of the anisotropic rare earth iron-boron-based sintered magnet cannot be sufficiently utilized, and thus it is difficult to realize a core material having a low iron loss. For this reason, the market demand for a high-output and high-efficiency BLDC motor capable of contributing to energy saving of automobiles by a synergistic effect of effective use of permanent magnet performance and reduction in iron loss of a core material is extremely high.
• the Fe-Si-B-based amorphous alloy has a higher magnetic permeability than that of a silicon steel sheet and can reduce the iron loss to about 1/10, an alternative to a silicon steel sheet has been studied as a core material of an EV drive BLDC motor.
• the saturation magnetic flux density (Bs) is low as described above, the Fe-Si-B-based amorphous alloy is mainly applied to a high-speed rotation type BLDC motor of 15,000 rpm or more in which the influence of iron loss becomes remarkable, and it is difficult to apply the Fe-Si-B-based amorphous alloy to a drive motor for EV having a rotation speed of less than 15,000 rpm.
• the Fe-Si-B-based amorphous alloy ribbon has a small thickness of about 25 ⁇ m, and it is difficult to perform punching press processing for producing a laminated core or the like for a rotor core and a stator core of a BLDC motor. Therefore, the Fe-Si-B-based amorphous alloy ribbon is mainly limited to use as a wound core, and it is difficult to replace a silicon steel sheet in motor applications.
• the Fe-Si-B-based nanocrystal material is only used as a wound core or molded after pulverization to be used as a dust core, and it is difficult to use the Fe-Si-B-based nanocrystal material as a laminated core similarly to the Fe-Si-B-based amorphous alloy.
• Non Patent Literature 1 discloses that the quench solidification rate is reduced by adding phosphorus (P), and an iron-based amorphous alloy ribbon having a thickness of 50 ⁇ m or more is obtained.
• P phosphorus
• the phosphorus component volatilizes at the time of melting the alloy, so that contamination inside and outside the molten metal quenching apparatus may become significant, and further, the phosphorus component may be likely to burn, and thus there are still few application examples in the industrial field.
• Patent Literatures 1 to 3 disclose a method for producing an amorphous alloy ribbon having a plate thickness (e.g., about 50 ⁇ m) at which punching processing can be performed by a multi-slit method in which a molten alloy is tapped onto a rotating cooling roll from a plurality of slit nozzles.
• a plate thickness e.g., about 50 ⁇ m
• Patent Literature 4 discloses a method for producing a metal ribbon in which the thickness of the metal ribbon is suppressed from becoming uneven when a wide quenched ribbon is fabricated using a porous nozzle.
• the invention of Patent Literature 4 is characterized by the shape of the nozzle opening, but there is a problem that the nozzle processing cost increases due to difficulty in processing, and it is difficult to use the invention at a mass production level.
• Patent Literature 5 discloses a method for producing an iron-based silicon boron-based amorphous alloy in which the thickness is increased using a tapping nozzle having a zigzag type multi-orifice, but it is difficult to ensure high Bs and a sufficient thickness as compared with a silicon steel sheet.
• Patent Literature 6 discloses an Fe-Si-B-based quench-solidified alloy capable of forming a laminated core characterized by having high Bs of Bs ⁇ 1.7 T and a thickness ⁇ 40 ⁇ m.
• the invention of Patent Literature 6 is obtained by optimizing the blending ratio of each element in a ternary composition of iron, silicon, and boron, which are essential elements, but since the workability of punching press when a laminated core is produced from an alloy ribbon obtained by this is inferior to that of a silicon steel sheet, there is room for further improvement in fabricating the laminated core at low cost.
• Non-Patent Literature 1 Creation of a novel bulk metallic glass/amorphous thick plate having a high saturation magnetic flux density (General Research Center for Metallic Glass, TOHOKU University) by Akihiro MAKINO, Ken KUBOTA, and Joshunto
• An object of the present invention is to provide a method for producing an iron-based crystal alloy capable of easily performing punching processing while ensuring a low iron loss and a high saturation magnetic flux density.
• the object of the present invention is achieved by a method for producing an iron-based crystal alloy, the method including: a step of preparing an (Fe,Co)-B-based molten alloy having a composition represented by a composition formula (Fe 1-y Co y ) 100-x (B 1-z C z ) x and in which x, y, and z satisfy 10.0 ⁇ x ⁇ 18.0 atom%, 0.05 ⁇ y ⁇ 0.5, and 0.0 ⁇ z ⁇ 0.3, respectively; and a quench solidification step of quench-solidifying the molten alloy on a cooling roll, wherein the quench solidification step includes a step of injecting the molten alloy onto a surface of the cooling roll from a tapping nozzle including a single-slit nozzle while rotating the cooling roll at a roll surface speed of 15 m/sec or more and 40 m/sec or less to fabricate an iron-based crystal alloy in which an abundance ratio of an ⁇ -Fe phase is 50 vol% or
• the tapping nozzle preferably has a slit width of 0.2 mm or more and 0.7 mm or less.
• a distance from the tapping nozzle to the surface of the cooling roll is preferably 0.2 mm or more and 5.0 mm or less.
• the present invention it is possible to provide a method for producing an iron-based crystal alloy capable of easily performing punching processing while ensuring a low iron loss and a high saturation magnetic flux density.
• the iron-based crystal alloy composition of the present invention is based on a binary alloy composition of Fe-B, in which a part of Fe is substituted with Co, which is a ferromagnetic element like Fe, and the composition formula is represented by (Fe 1-y Co y ) 100-x (B 1-z C z ) x .
• B is an element essential for obtaining a low iron loss and a high magnetic permeability, and plays a role in forming a structure consisting of an ⁇ -Fe phase and an Fe-B phase into a uniform microstructure.
• a part of B may be substituted with C, and this reduces the melting point of the molten alloy, so that the quench solidification conditions are relaxed, and the iron-based crystal alloy is easily fabricated.
• z in the above composition formula is 0.0 ⁇ z ⁇ 0.3, and from the viewpoint of maintaining high Bs characteristics, 0.0 ⁇ z ⁇ 0.2 is preferable, and 0.05 ⁇ z ⁇ 0.15 is more preferable.
• x in the above composition formula is 10.0 ⁇ x ⁇ 18.0 atom%, and 11.0 ⁇ x ⁇ 17.0 atom% is preferable, and 12.0 ⁇ x ⁇ 16.0 atom% is more preferable.
• the iron-based crystal alloy of the present invention is an (Fe,Co)-B-based iron-based crystal alloy having a composite structure of an ⁇ -Fe phase and an Fe-B phase, and has magnetic properties and mechanical properties that greatly contribute to improvement in efficiency of a BLDC motor. If the abundance ratio of the ⁇ -Fe phase is too low, it is difficult to ensure Bs ⁇ 1.7 T. On the other hand, if the abundance ratio is too high, coarse ⁇ -Fe of about 10 ⁇ m or more is likely to precipitate, and thus there is a possibility that the coarse ⁇ -Fe becomes a starting point of cracking during punching press, and further, an increase in iron loss and a decrease in magnetic permeability are likely to occur.
• the abundance ratio of the ⁇ -Fe phase is 50 vol% or more and less than 95 vol%, preferably 60 vol% or more and less than 90 vol%, and more preferably 60 vol% or more and less than 85 vol%.
• the Fe-B phase is a remaining phase of the ⁇ -Fe phase, and is a phase mainly composed of FeB and Fe2B.
• the abundance ratio and the crystal grain size of the ⁇ -Fe phase can be adjusted to desired values by controlling the quenching rate of the molten alloy.
• the average crystal grain size of the ⁇ -Fe phase is preferably 2 nm to 20 nm.
• the average crystal grain size of the ⁇ -Fe phase can be determined from the half width of an X-ray diffraction peak by powder X-ray diffraction (XRD) described later.
• the saturation magnetic flux density of the iron-based crystal alloy of the present invention is Bs ⁇ 1.7 T, but when it is assumed that an EV drive BLDC motor of 30 kW or more is applied, Bs ⁇ 1.72 T is preferable, and Bs ⁇ 1.75 T is more preferable.
• the iron-based crystal alloy of the present invention has an iron loss (W10/1k) of ⁇ 20 W/kg at a magnetic flux of 1.0 T and a frequency of 1 kHz, and has low iron loss performance that is significantly lower than an iron loss (W10/1k) of a silicon steel sheet (JIS standard 35A360) of 96.6 W/kg.
• the iron loss (W10/1k) exceeds 20 W/kg, the effect of improving the motor efficiency decreases.
• an iron loss (W10/1k) of ⁇ 15 W/kg is preferable, and an iron loss (W10/1k) of ⁇ 10 W/kg is more preferable.
• the iron-based crystal alloy of the present invention has a magnetic permeability of 1500 or more at 1 kHz. If the magnetic permeability is lower than 1500 at 1 kHz, the superiority of the magnetic flux amount on the surface of the teeth portion in the stator core over the silicon steel sheet is reduced. In order to further enhance the superiority over the silicon steel sheet, the magnetic permeability is preferably 2000 or more, and more preferably 3000 or more at 1 kHz.
• the iron-based crystal alloy of the present invention is produced by a method for producing an iron-based crystal alloy including a step of preparing an (Fe,Co)-B-based molten alloy having the above composition, and a quench solidification step of quench-solidifying the prepared molten alloy.
• FIG. 1 is a schematic configuration diagram of a single-roll molten metal quenching apparatus used in a method for producing an iron-based crystal alloy according to an embodiment of the present invention.
• the single-roll molten metal quenching apparatus 1 illustrated in FIG. 1 includes a melting furnace 2, a molten metal storage container 5, and a cooling roll 8.
• the melting furnace 2 supplies a molten alloy 3 in which a raw material is melted by high-frequency induction heating to the molten metal storage container 5 by rotation of a tilting shaft 4.
• the molten metal storage container 5 includes a tapping nozzle 6 at the bottom, further heats the molten alloy 3 by a heating coil (not illustrated), and jets the molten alloy 3 from a slit 7 formed at the lower end of the tapping nozzle 6 to the surface (outer peripheral surface) of the cooling roll 8.
• the material of the tapping nozzle 6 can be appropriately selected from, for example, quartz (SiO 2 ), boron nitride (BN), silicon carbide (SiC), and alumina (Al 2 O 3 ).
• FIG. 2 is an enlarged view illustrating the tapping nozzle 6 of the apparatus illustrated in FIG. 1 , in which FIG. 2(a) is a cross-sectional view and FIG. 2(b) is a bottom view.
• the tapping nozzle 6 illustrated in FIG. 2(a) is a single-slit nozzle in which a single slit 7 is formed.
• the width W1 of the slit 7 serves to adjust the tapping rate of the molten alloy 3 supplied to the cooling roll 8. If the slit width W1 is too small, slit processing is likely to be difficult, and further, the slit 7 is likely to be blocked by the molten metal.
• the slit width W1 is 0.2 mm or more and 0.7 mm or less.
• the slit width W1 is preferably 0.3 mm or more and 0.6 mm or less, and more preferably 0.3 mm or more and 0.5 mm or less.
• the molten metal supplied to the surface of the cooling roll 8 becomes the quench-solidified alloy 9 having a ribbon shape by rotation of the cooling roll 8, and is peeled off from the cooling roll 8. If the surface speed of the cooling roll 8 is too low, an (Fe,Co)-B-based quench-solidified alloy having an excessive thickness exceeding 50 ⁇ m is formed, so that a coarse ⁇ -Fe phase precipitates, and cracking is likely to occur during punching press. On the other hand, if the surface speed of the cooling roll 8 is too high, miniaturization of the (Fe,Co)-B-based crystal alloy proceeds too much, and the abundance ratio of an ⁇ -Fe phase decreases, so that it tends to be difficult to ensure Bs ⁇ 1.7 T.
• the surface speed of the cooling roll 8 is 15 m/sec or more and 40 m/sec or less, preferably 15 m/sec or more and 35 m/sec or less, and more preferably 17 m/sec or more and 32 m/sec or less.
• the diameter of the cooling roll 8 is, for example, 200 to 20000 mm.
• Water cooling is not necessarily required for the cooling roll 8 as long as the quench solidification time is a short time of 10 sec or less. However, when the quench solidification time is 10 sec or more, it is preferable to suppress the temperature rise of the surface of the cooling roll 8 by allowing cooling water to flow inside the cooling roll 8.
• the water cooling capacity of the cooling roll 8 is preferably appropriately adjusted according to the latent heat of solidification per unit time and the tapping rate.
• the adhesion of the molten alloy 3 to the outer surface of the cooling roll 8 is important, and the molten metal adhesion largely depends on the surface roughness of the cooling roll 8. If the surface roughness of the cooling roll 8 is too small, the molten alloy 3 slides on the surface of the cooling roll 8, so that sufficient cooling becomes difficult. On the other hand, if the surface roughness of the cooling roll 8 is too large, there is a possibility that the quenched alloy sticks to the cooling roll 8.
• the arithmetic average roughness (Ra) of the surface of the cooling roll 8 is 0.01 ⁇ m or more and 0.6 ⁇ m or less, preferably 0.05 ⁇ m or more and 0.55 ⁇ m or less, and more preferably 0.1 ⁇ m or more and 0.5 ⁇ m or less.
• the above distance d is 0.2 mm or more and 5.0 mm or less, preferably 0.3 mm or more and 3.0 mm or less, and more preferably 0.3 mm or more and 2.0 mm or less.
• the cooling roll 8 is preferably excellent in thermal conductivity and durability by being formed of a material containing any one of pure copper, a copper alloy, molybdenum (Mo), and tungsten (W) as a main raw material.
• the main raw material means that the material accounts for 50% or more by weight.
• the surface of the cooling roll 8 may be plated with chromium, nickel, or an alloy thereof, thereby being able to increase the heat resistance and hardness of the surface of the cooling roll 8 and to suppress melting and deterioration of the surface of the roll during quench solidification.
• an (Fe,Co)-B-based quench-solidified alloy is heat-treated at a constant temperature of 200°C or more and 700°C or less, so that strain in the quench-solidified alloy can be removed, and further reduction in iron loss can be realized. If the heat treatment temperature is lower than 200°C, the effect of strain removal is small. If the heat treatment temperature exceeds 700°C, coarsening of an ⁇ -Fe phase proceeds, so that brittleness of the quench-solidified alloy increases, and the quench-solidified alloy is likely to crack during punching processing.
• the above heat treatment temperature is preferably 300°C or more and 700°C or less, and more preferably 400°C or more and 680°C or less.
• the heat treatment time of the above heat treatment depends on the shape of the soaking zone of the heat treatment apparatus, and an optimum heat treatment time is appropriately selected within a time range of 3 minutes or more and less than 2 hours.
• the above heat treatment is preferably performed in a vacuum or inert gas atmosphere, but heat treatment in the atmosphere is also allowed.
• alumina crucible (melting furnace) 100 kg of a raw material in which respective elements of B, C, Co, and Fe having a purity of 99.5% or more were blended so as to have an alloy composition shown in Examples 1 to 11 and Comparative Examples 12 to 17 in the following Table 1 was housed, and was melted by high-frequency induction heating to form a molten alloy. Fifty kilograms (50 kg) of the molten alloy was poured into a molten metal storage container made of alumina having an inner diameter of 200 mm ⁇ a height of 400 mm and including a BN tapping nozzle having a slit shown in Table 1 at the bottom. The slit width and the slit length of the tapping nozzle are as shown in Table 1.
• the molten alloy was jetted from the tapping nozzle to the surface of the cooling roll immediately below.
• the cooling roll is made of chromium zircon copper, and has an outer diameter of 600 mm and a width of 200 mm.
• the gap between the tapping nozzle and the surface of the cooling roll is as shown in Table 1.
• the injection pressure of the molten alloy from the tapping nozzle, the roll surface speed of the cooling roll, and the arithmetic average roughness (Ra) of the roll surface of the cooling roll are as shown in Table 2.
• the molten alloy jetted onto the surface of the cooling roll formed a lump of molten metal (puddle) on the surface of the cooling roll, and was quench-solidified at the interface between the puddle and the cooling roll to obtain a quench-solidified alloy having a ribbon shape and an average thickness and an average width shown in Table 3.
• the quench-solidified alloy was subjected to heat treatment at 650°C for 10 minutes in an Ar flow gas.
• the quench-solidified alloy thus obtained was subjected to a punching test, the results shown in Table 3 were obtained.
• the quench-solidified alloy thus obtained was subjected to structure evaluation by powder X-ray diffraction (XRD), and as a result, the quench-solidified alloys of Examples 1 to 11 were all crystal alloys consisting of ⁇ -Fe type and Fe-B type compounds.
• the vol% of ⁇ -Fe precipitated in the quench-solidified alloy (the abundance ratio of ⁇ -Fe was determined by X-ray diffraction) is shown in Table 3.
• Quantitative analysis of constituent phases by powder X-ray diffraction is a general evaluation method, and is incorporated into analysis software of an X-ray diffractometer, and it is possible to grasp the composition ratio of each phase.
• Examples 4 and 9 are shown in FIGS. 3 and 4 , respectively.
• the structures of the quench-solidified alloys of Examples 4 and 9 were composite structures consisting of an ⁇ -Fe phase and an Fe-B phase.
• Bs, iron loss, and magnetic permeability of the as-spun (immediately after quench solidification) quench-solidified alloys or the quench-solidified alloys after heat treatment of Examples 1 to 11 and Comparative Examples 12 to 17 are shown in Table 4.
• Bs was measured using a vibrating sample magnetometer manufactured by Toei Industry Co., Ltd., and iron loss and magnetic permeability were measured using a B-H analyzer manufactured by Iwatsu Electric Co., Ltd.
• the powder X-ray diffraction profile of the quench-solidified alloy of Example 3 was also a composite structure consisting of an ⁇ -Fe phase and an Fe-B phase.
• the quench-solidified alloys of Comparative Examples 12 to 17 had a metal structure of an amorphous single phase as evaluated by powder X-ray diffraction (XRD).
• Table 3 shows the vol% of ⁇ -Fe (the abundance ratio of ⁇ -Fe was determined by X-ray diffraction).
• Comparative Example 12 is shown in FIG. 6 .
• the structure of the quench-solidified alloy of Comparative Example 12 was an amorphous single phase structure.

Landscapes

• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Mechanical Engineering (AREA)
• Materials Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Physics & Mathematics (AREA)
• Electromagnetism (AREA)
• Dispersion Chemistry (AREA)
• Power Engineering (AREA)
• Continuous Casting (AREA)
• Soft Magnetic Materials (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)

Applications Claiming Priority (2)

Publications (1)

Family

ID=89771002

Family Applications (1)

Country Status (6)

Families Citing this family (3)

Citations (6)

Family Cites Families (4)

• 2023
  • 2023-07-21 JP JP2023119069A patent/JP7429078B1/ja active Active
• 2024
  • 2024-07-11 KR KR1020257039509A patent/KR20260046292A/ko active Pending
  • 2024-07-11 WO PCT/JP2024/025071 patent/WO2025023038A1/fr active Pending
  • 2024-07-11 CN CN202480038039.4A patent/CN121335994A/zh active Pending
  • 2024-07-11 AU AU2024299016A patent/AU2024299016A1/en active Pending
  • 2024-07-11 EP EP24845419.1A patent/EP4685249A1/fr active Pending

Patent Citations (6)

Non-Patent Citations (1)

Also Published As

Similar Documents

Legal Events