EP2540845A1 - Metallisches material als feste lösung für ein kubisch-innenzentriertes gitter mit gesteuerter kristallachsen-ausrichtung und herstellungsverfahren dafür - Google Patents

Metallisches material als feste lösung für ein kubisch-innenzentriertes gitter mit gesteuerter kristallachsen-ausrichtung und herstellungsverfahren dafür Download PDF

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Publication number
EP2540845A1
EP2540845A1 EP11747563A EP11747563A EP2540845A1 EP 2540845 A1 EP2540845 A1 EP 2540845A1 EP 11747563 A EP11747563 A EP 11747563A EP 11747563 A EP11747563 A EP 11747563A EP 2540845 A1 EP2540845 A1 EP 2540845A1
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European Patent Office
Prior art keywords
solid solution
bcc
metallic material
crystal
centered cubic
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EP11747563A
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English (en)
French (fr)
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EP2540845A4 (de
Inventor
Hiroshi Fukutomi
Kazuto Okayasu
Yusuke Onuki
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Yokohama National University NUC
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Yokohama National University NUC
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • H01F1/16—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 in the form of sheets
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation

Definitions

  • This invention relates to a metallic material as a solid solution having a body-centered cubic (BCC) structure, an orientation of crystal axis ⁇ 001> of which is controlled in a plane, and a method of manufacturing the material, for example an electromagnetic material used for an iron core of an electric device, and the method of manufacturing the material.
  • BCC body-centered cubic
  • An electrical steel sheet used widely in electric devices is an example of a material which can perform large effect of technical features by aligning crystal axis of a metal.
  • a direction of magnetic field as a transformer shown in Fig. 3 is fixed, a grain-oriented electrical steel sheet, in which crystal axis is controlled, is used.
  • magnetic lines of force shown with dot lines 33 in Fig. 3 are provided in a plane of core sheets 31, which are stacked to be aligned in a direction of easy magnetization
  • a single phase SRM switched reluctance motor shown in Fig. 4 includes a stator 10, which a coil connected with an outer electric power is wound, and a rotor 20 provided rotatably in the stator 10 and rotated by electromagnetic forces acting between the stator 10 and the rotor 20 when outer electric power is supplied to the stator 10.
  • the stator 10 includes a yoke 12 having a ring shape, a plurality of poles 16 projecting along a radial direction from the yoke 12 toward the rotor 20 at an interval to each other through a predetermined slot 14 along a circumference of the yoke 12, and a coil 18 would around the pole 16 and connected with the outer electric power.
  • the stator 10 of the motor is manufactured by steps of punching a stator sheet having a plane shape with the yoke 12 and the pole 16 from a thin electrical steel sheet, stacking the stator sheets to be an iron core having a predetermined height, and winding a coil 18 around the magnetic core.
  • Magnetization of steel has anisotropic property according to a crystal axis. Magnetization along the axis ⁇ 001> is acted most easily with small hysteresis loss. Magnetisation along the axis ⁇ 011> is acted next most easily with small hysteresis loss. Magnetization along the axis ⁇ 111> is acted in most difficulty with large hysteresis loss. Therefore, for a rotor and a stator of a motor, the orientation of the axis ⁇ 001> is mainly aligned preferably along a radial direction of the motor so as to magnetize it easily and reduce core loss by hysteresis. Thus, core material, which orientation of the axis ⁇ 001> is aligned rotational-symmetrically about an axis of a motor, is expected.
  • non-oriented electrical steel sheet made of silicon steel and having isotropic property in 3-dimensions as shown in Fig. 5 is developed and delivered by Nippon Steel Corporation, and JFE Steel. Electrical steel sheet named by Hi-light core (trade name) and Home core (trade name) is supplied.
  • a direction of easy magnetization is eccentrically arranged not in a certain direction in the steel sheet, but many crystal axes ⁇ 001> as an axis of easy Magnetization are not arranged along a surface of steel sheet. Thereby, magnetic flux density along the surface of the steel sheet can not be increased, and improving efficiency of motor is limited.
  • Patent Document 1 Japan Patent Application Published No. 2006-87289
  • Unpatent Document 1 NIPPON STEEL MONTHLY April 2005, P. 11-14
  • a metal having a face-centered cubic (FCC) structure such as aluminum
  • FCC face-centered cubic
  • BCC body-centered cubic
  • the usual uniaxial compression process has a problem that not only crystal plane ⁇ 100 ⁇ arranging crystal axis ⁇ 001> having excellent magnetic property in parallel to the surface of the steel sheet, but also crystal plane ⁇ 111 ⁇ unable to arrange crystal axis ⁇ 001> in the surface of the steel sheet exist together.
  • the usual uniaxial compression process develops crystal plane ⁇ 111 ⁇ in the surface more than crystal plane ⁇ 100 ⁇ , so that the uniaxial compression process is not applied as a method for manufacturing electrical steel sheet so as to arrange crystal axis ⁇ 001> along a surface of the sheet.
  • an object of the present invention is to control crystal axis of metal.
  • the object is to control axis of easy magnetization ⁇ 001> of an iron based material along a work surface of manufacturing process.
  • the object is to provide a metallic material having excellent magnetic property of easy magnetization along a surface of a sheet and large magnetic flux density and small core loss by controlling the axis of easy magnetization ⁇ 001> along the work surface of manufacturing process, and a method of manufacturing the metallic material.
  • crystallographic texture including crystal plane ⁇ 110 ⁇ is formed by uniaxial compression deformation of Al-Mg solid solution alloy having FCC structure in high temperature.
  • present inventors found that with increasing amount of deformation, the crystal plane ⁇ 100 ⁇ develops, and after that, the crystallographic texture becomes to be formed by only crystal plane ⁇ 100 ⁇ .
  • ⁇ 100 ⁇ was the orientation with low Taylor factor, which corresponded to the total amount of shear strain and thus the amount of dislocation was considered to be small. Furthermore, it was noticed that ⁇ 100 ⁇ is stable orientation for deformation.
  • the present inventor had a thought that in a solid solution having body-centered cubic (BCC) structure, different crystallographic texture from that of pure metal would be generated.
  • BCC body-centered cubic
  • the present inventor focused that different from that of FCC metal, ⁇ 100 ⁇ and ⁇ 111 ⁇ coexists at room temperature due to difference in slip systems, and Taylor factor of crystal plane ⁇ 100 ⁇ is lower than Tailor factor of crystal plane ⁇ 111 ⁇ .
  • the present inventor reached to have an idea that when process condition, in which solute atmosphere dragging of dislocation becomes dominant deformation mechanism and grain boundary migration become possible, could be found, technology of manufacturing process for material, by which ⁇ 111 ⁇ would be disappeared and oppositely ⁇ 100 ⁇ is frequently arranged along the surface of the sheet material, would be developed.
  • a usual method of manufacturing non-oriented electrical steel sheet is formed by combining two processes of cold working and heat treatment, or hot working and heat treatment, and in contrast, based on the above found phenomena, it was appeared that electrical steel sheet, which can be controlled so as to align axes of easy magnetization ⁇ 001> along a work surface of manufacturing process, by only one process of hot uniaxial compression process or hot plane strain compression process, can be manufactured.
  • the present invention is accomplished.
  • the present invention is a method for manufacturing metallic material as a solid solution having a body-centered cubic (BCC) structure, in which the metallic material is formed by hot compression process in a temperature range, in which the metallic material becomes BCC single phase solid solution, so as to arrange crystal axis ⁇ 001> along a work surface of manufacturing process of the metallic material.
  • BCC body-centered cubic
  • crystal axis. ⁇ 001> of the metal can be distributed along the work surface of manufacturing process without heat treatment after the manufacturing process, so that principle of the present invention can be applied for a metallic material as a solid solution having body-centered cubic (BCC) structure, and it has varied applications.
  • BCC body-centered cubic
  • the present invention is a method for manufacturing metallic material, for example electrical steel sheet, having steps of: heating Fe-Si alloy as the metallic material in a temperature range to be BCC single phase solid solution, and applying compression process on the BCC solid solution with a strain rate able to maintain process condition in which solute atmosphere generated in the BCC single phase solid solution dominates dislocation motion and grain boundary can migrate by strain energy stored in a crystal grain as driving force so as to distribute ⁇ 100 ⁇ in parallel to a work surface of manufacturing process.
  • the crystal plane ⁇ 100 ⁇ can be arranged in parallel to a work surface of manufacturing process.
  • crystal axis ⁇ 001> is distributed along the work surface of manufacturing process.
  • the present invention is a method for manufacturing a metallic material in which Fe-Si alloy is used as the solid solution having the body-centered cubic (BCC) structure; and the Fe-Si alloy is heated in temperature range to become BCC single phase solid solution and compression process with strain rate from 1 ⁇ 10 -5 /s to 1 ⁇ 10 -1 /s is applied to the Fe-Si alloy.
  • BCC body-centered cubic
  • the strain rate able to maintain process condition in which solute atmosphere generated in the BCC single phase solid solution can control motion of dislocations and grain boundary can migrate by strain energy stored in a crystal grain as driving force is in range from 1 ⁇ 10 -5 /s to 1 ⁇ 10 -1 /s.
  • the crystal plane ⁇ 100 ⁇ can be distributed in parallel to the work surface of manufacturing process.
  • an electrical steel sheet of Fe-Si alloy having good properties is manufactured.
  • the Fe-Si alloy includes preferably Si of 1-7 weight%, and Fe remaining and unavoidable impurities.
  • the present invention is further characterized in that the temperature range is between 800-1300°C.
  • the present invention is further characterized in that total amount of strain of at least -0.5 is given at the single phase solid solution having the body-centered cubic (BCC) structure by the compression process.
  • BCC body-centered cubic
  • a high-quality electrical steel sheet in which crystal axis ⁇ 001> is securely controlled along a surface of the sheet, can be provided.
  • the ⁇ 100 ⁇ compression plane
  • the ⁇ 100 ⁇ is a crystal orientation with low strain energy under uniaxial compression deformation, and the crystal arranged in the orientation is stable against deformation, so that migration of grain boundary is acted during deformation so as to increase grain size of the crystal. Therefore, when the amount of strain is increased, ⁇ 100 ⁇ fiber texture develops. Larger strain provides better results.
  • ⁇ 100 ⁇ parallel to the work surface of manufacturing process grows remarkably.
  • the present invention is also related to a metallic material as a solid solution having the body-centered cubic (BCC) structure, in which crystal axes ⁇ 001> are distributed along a work surface of manufacturing process by hot compression process.
  • ODF crystal Orientation Distribution Function
  • ODF crystal Orientation Distribution Function
  • ODF crystal Orientation Distribution Function
  • the electrical steel sheet by Fe-Si alloy in which the distribution of the crystal axis ⁇ 001 ⁇ is controlled so as to be in parallel to the work surface of manufacturing process, has better properties comparing usual non-oriented electrical steel sheet.
  • the metallic material in which the crystal axis is controlled especially, the electrical steel sheet, in which axis of easy magnetization ⁇ 001> is controlled to be aligned along the work surface of manufacturing process, is provided, so that the electrical steel sheet having excellent magnetic properties with large magnetic flux and small core loss is supplied.
  • Embodiments of an electrical steel sheet and a method for manufacturing the steel sheet according to the present invention will be described as following.
  • One of phenomena affecting mainly the movement of dislocation is a dragging of a solute atmosphere generated in a solid solution alloy under combination of a certain temperature range and a strain rate.
  • the phenomenon is that the dislocation. surrounded by the solute atoms moves together with the solute atoms.
  • Si as the solute atom forms the solute atom atmosphere existing at higher density than an average density in overall crystal around the dislocation.
  • the dislocation can not break away from the solute atom atmosphere and move with dragging the dislocation. Thereby, velocity of the dislocation is slowed by dragging the solute atom atmosphere.
  • the dislocation is distributed uniformly in the crystal.
  • the dislocation dragging the solute atmosphere is easily distributed uniformly in the crystal.
  • the dislocation is a lattice defect and has strain energy.
  • an amount of dislocations contributing to its deformation is varied.
  • the amount of dislocation is different from each crystal, and in result, amount of energy stored in each crystal is varied.
  • dislocations are distributed so as to cancel strain energy of each crystal to each other. Difference of dislocation densities about each crystal grain is not directly reflected to difference of the strain energy stored in each crystal grain.
  • the orientation of crystal having low strain energy under uniaxial compression deformation of a solid solution having the body-centered cubic (BCC) structure is ⁇ 100 ⁇ (surface of sheet).
  • the orientation of crystal under plane strain compression deformation such as rolling is ⁇ 001> (extending direction) in ⁇ 100 ⁇ (surface of plane). Therefore, the crystal grains in the orientation of crystal consume other crystal grains in other orientations, and grow.
  • the crystal in the orientation of crystal plane ⁇ 100 ⁇ is stable against compression deformation, so that during deformation, the grain boundary migrates so as to grow the crystal grain. Therefore, when increasing the strain, fiber texture ⁇ 100 ⁇ is growing at uniaxial compression deformation, and ⁇ 100 ⁇ 001> texture is growing at plane strain compression deformation.
  • ⁇ 100 ⁇ shows a work surface of manufacturing process
  • ⁇ 001> shows an extending direction by rolling.
  • ⁇ 100 ⁇ is arranged in parallel to a sheet surface under both of uniaxial compression deformation and plane strain compression deformation.
  • the crystal plane ⁇ 100 ⁇ is arranged in parallel to the surface of plate.
  • ⁇ 001> is distributed uniformly in high density in a direction vertical to a direction of compression in the surface of the plane around the crystal axis ⁇ 100> as a normal of the crystal plane ⁇ 100 ⁇ as a rotation axis.
  • plane strain deformation such as rolling, when a thickness of the sheet is reduced by compression process, the sheet extends in one direction.
  • crystal axis ⁇ 001> is distributed in high density along extending direction.
  • an Fe-Si alloy which includes at least Si and Fe remaining and unavoidable impurities, is heated in a temperature range in which the alloy becomes solid solution having body-centered cubic (BCC) structure.
  • the solid solution having the body-centered cubic (BCC) structure is processed by the uniaxial compression process or the plane strain compression process with a strain rate which can maintain a process condition which the movement of dislocation dragging the solute atmosphere generated in the BCC solid solution becomes main deformation mechanism, and the grain boundary of the crystal can migrate by the strain energy stored in the crystal grain as a driving force.
  • the crystal plane ⁇ 100 ⁇ is distributed in high density in parallel to the work surface.
  • the temperature range is between 800-1300°C, and the strain rate is between 10 ⁇ 10 -5 -1 ⁇ 10 -1 /s.
  • the total amount of strain applied on the solid solution having body-centered cubic (BCC) structure by compression process is more than -0 . 5 as a true strain.
  • the purposed condition is simply widened according to increasing amount of strain, but is not enough when the amount of strain is small. Larger amount of strain generates better condition, so that amount of strain is not upper-limited, and also, the strain can be applied divisionally.
  • the solid solution having body-centered cubic (BCC) structure can be BCC single phase solid solution which is formed by not only binary alloy, but also ternary or more alloy including a component other than Si.
  • the solid solution having body-centered cubic (BCC) structure is Fe-Si alloy
  • content of Si is in range between 1-7 weight%.
  • the content of Si is not larger than 1 weight%, the alloy cannot have enough specific resistance for low core loss.
  • the content of Si is more than 7 weight%, crack is increased in compression process, so that compression process becomes troublesome.
  • Content of Si is preferably between 1 weight% at the lowest and 7 weight% at the highest.
  • C, Mn, P, S, Al and N are listed.
  • Mn reacts with S to each other so as to extract fine sulfide MnS and deteriorates extremely magnetic properties.
  • P inhibits manufacturability.
  • Mn and P should be controlled less than 0.01 weight%.
  • S, which inhibits growing crystal grain, should be controlled less than 0.0001 weight%.
  • Fe-Si alloy which is used as the solid solution having the body-centered cubic (BCC) structure, is heated in temperature range between 800-1300°C to become BCC single phase.
  • Fe-Si alloy having Si content of 2-5 weight% has BCC structure always in temperature range from a low temperature to melting point.
  • Fe-Si alloy having Si content less than 2 weight% changes once to FCC structure in high temperature according to the content of Si, so that growing of fiber texture ⁇ 100 ⁇ may be inhibited.
  • Fe-Si alloy having Si content less than 2 weight% is heated in lower temperature area in the temperature range between 800-1300°C to become BCC single phase.
  • the strain rate in compression process for BCC single phase solid solution shows amount of strain per unit time, that is process speed.
  • the process speed which is low or high, changes main mechanism controlling movement of dislocation affecting the deformation. Therefore, the process speed is limited so as to maintain the process condition, in which solute atmosphere generated in the BCC solid solution controls the motion of dislocation in temperature range of heating solid solution having the body-centered cubic (BCC) structure so as to be BCC single phase.
  • the strain rate of Fe-Si alloy as the solid solution having body-centered cubic (BCC) structure is determined between 1 ⁇ 10 -5 -1 ⁇ 10 -1 /s in the temperature range between 800-1300°C.
  • the texture of Fe-Si alloy having Si content of 3 weight% was evaluated in strain rate range between 1 ⁇ 10 -5 -1 ⁇ 10 -2 /s in the temperature 900°C, and in strain rate range between 1 ⁇ 10 -4 -1 ⁇ 10 -2 /s in the temperature 1250°C. It is assumed that when the strain rate is the same, the temperature in process condition, which the same crystal structure is generated, is changed to lower according to increasing Si content; and when the temperature is the same, the strain rate in process condition, which the same crystal structure is generated, is changed to higher according to increasing Si content.
  • the above strain rate of Fe-Si alloy is determined about uniaxial compression process in the above range of Si content and the temperature range based on the above assumption.
  • the solid solution having body-centered cubic (BCC) structure as a material is formed by steps of hot rolling (heating temperature 1100°C ⁇ 60minutes and finish temperature higher than 850°C) a 40Kg ingot made by vacuum melting into 40mm thick, cutting that into 320mm length, hot rolling that (heating temperature 1100°C ⁇ 60minutes and finish temperature higher than 850°C) into 20mm thick, cutting into a plate of 20mm thick, 140mm wide, 290mm length, and forming that into a cylindrical steel piece with round cross-section of 12mm diameter and 18mm height by electro-discharge machining.
  • the ingots A, B, C and D are formed to have Si of 1.5, 3, 4, and 5 weight%; Mn and P less than 0.01 weight%, and S less than 0.01 weight% as unavoidable impurities.
  • the four materials A, B, C and D include C, Al and N of weight% shown in Table 1 as unavoidable impurities other than Mn, P and S by knowing a content by composition analysis after process shown in Table 1.
  • Each of the above content steel pieces heated at 900°C or 1250°C in a heat furnace is formed into a steel piece with 20mm diameter and 6.6mm height at strain rate range between 1 ⁇ 10 -5 -5 ⁇ 10 -2 /s to have true strain of -1.0% by uniaxial compression process, and the steel piece is cooled gradually in room temperature air.
  • Cross-head speed constant function of a tension tester having load capacity of 2 ton shown in Fig. 7 (Shimazu Autograpgh as trademark) is used for uniaxial compression process.
  • a cylindrical compression jig is arranged upside and downside the tester, and the steel piece is provided between the compression jigs, and load is applied from upside and downside.
  • the upper and lower jigs and the steel piece are arranged in the heat furnace.
  • the heater is illustrated as a heater.
  • a divided surface is polished and measured about distribution of orientation of crystal by Schulz Reflection Method as X-ray diffraction analysis, and thereby, crystal Orientation Distribution Function (ODF) is given.
  • ODF crystal Orientation Distribution Function
  • ⁇ , ⁇ 1 , ⁇ 2 are Euler angles.
  • Contour lines along an upper side and a lower side of a quadrangle show a distribution of the crystal orientation density in the surface of steel sheet.
  • a value of the contour line shows orientation density indicated by a multiple about an average value as 1.
  • the contour lines of value 18, 16, 14, 12, 10, 8, 6, 4 are drawn in order between the contour line of value 20 and the contour line of value 1.
  • concentration over value 14 is found even at a lowest area.
  • High density ⁇ 100 ⁇ fiber texture is formed therein. The value is an excellent value much more than a value of usual non-oriented electrical steel sheet shown in Fig. 2 .
  • orientation density along an upper side is between 0.5-2.0, so that it can be found that there is almost no texture.
  • crystal orientation distribution of the material before processing is not described.
  • the ⁇ 100 ⁇ fiber texture in which ⁇ 100 ⁇ is arranged in parallel to the work surface, is formed by hot compression process.
  • Any steel material having the same crystal orientation distribution as the usual non-oriented electrical steel sheet can be applied.
  • the material in the above embodiment is formed into a round cross-section, but, the material can be a plate or cylinder having a rectangular or polygonal cross-section other than round shape.
  • the surface processed by uniaxial compression process can have any shape other than a flat surface by the same reason.
  • Fig. 12 shows a model of BCC structure.
  • the BCC structure has symmetry about Up-down and right-left.
  • Axes [100], [010] and [001] shown in Fig. 12 are equivalent, and general term for the three axes is shown by ⁇ 001>. All surfaces of a cubic are equivalent and surfaces ⁇ 001 ⁇ , ⁇ 100 ⁇ and ⁇ 010 ⁇ are the same.
  • Fig. 13A The directions of easy magnetization of the usual non-oriented electrical steel sheet for a stator of a motor are shown in Fig. 13A .
  • directions of easy magnetization direct at any angle three-dimensionally.
  • Fig. 13B directions of easy magnetization in an almost ideal electrical steel sheet are shown.
  • Figs. 14A and 14B Distribution of directions of easy magnetization ⁇ 001> by ⁇ 100 ⁇ pole figure is shown in Figs. 14A and 14B.
  • Fig. 14A shows distribution of ⁇ 001> of the usual non-oriented electrical steel sheet.
  • Fig. 14B shows distribution of ⁇ 001> of the electrical steel sheet according to the present invention.
  • Values in the figures show concentration ratio of orientation density ⁇ 001> about average value 1.
  • the smallest value at an outer area much affecting the properties is not larger than 0.8 times of an average value.
  • the smallest value at the outer area is not less than 1.6 multiple of the average value, and the value at central area is more than 19 multiple of the average value.
  • ⁇ 001> density at the outer area becomes larger than that of usual material by prior art.
  • Fig. 15 shows a magnetic property of the electrical steel sheet according to the present invention.
  • a magnetic property of usual non-oriented electrical steel sheet is shown with a dot line in Fig. 15
  • a magnetic property of the electrical steel sheet according to the present invention is shown with a solid line in Fig. 15 .
  • larger magnetic flux density about added magnetic field is generated, so that it is expected that properties of an electromagnetic device such as a motor can be improved.
  • example of processing single material by uniaxial compression process is shown.
  • sheets by overlapping various materials can be simultaneously processed by compression process by a compression machine having larger load capacity. Also, sizes of material can be increased.
  • the rolling process shown in Fig. 9 can be applied.
  • crystal plane ⁇ 100 ⁇ grows in parallel to roll surface, so that the sheet, in whichmany crystal axes ⁇ 001> are distributed along rolling direction, can be given.
  • multi-directions rolling shown in Fig. 10 many crystal axes ⁇ 001> are distributed in many directions in the surface of sheet. Thus, the same effects of uniaxial compression process can be give.
  • a wire-shaped metal material can be formed by passing a row material through a die as shown in Fig. 11 under heat condition. ⁇ 001> of the material are aligned along a drawing direction, so that when magnetic flux flows along the drawing direction, good magnetic property can be given.
  • Fe-Si alloy as electromagnetic material is exampled.
  • the present invention can applied to all metallic material which can be processed in condition of body-centered cubic (BCC) structure by hot compression process.
  • BCC body-centered cubic
  • a metallic material, in which ⁇ 100 ⁇ grows in parallel to a work surface by hot compression process, can be formed.
  • a method of manufacturing process for a metallic material such as an electromagnetic material, in which orientation of crystal axis is controlled, is determinated, so that an electromagnetic material having good properties is provided, and energy loss of electromagnetic act is increased, and cost down can be performed and support environmental problems.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Soft Magnetic Materials (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
EP11747563.2A 2010-02-26 2011-02-28 Metallisches material als feste lösung für ein kubisch-innenzentriertes gitter mit gesteuerter kristallachsen-ausrichtung und herstellungsverfahren dafür Withdrawn EP2540845A4 (de)

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JP2010042132 2010-02-26
PCT/JP2011/054548 WO2011105609A1 (ja) 2010-02-26 2011-02-28 結晶軸＜００１＞の方位が制御された体心立方（ｂｃｃ）構造の固溶体である金属材料およびその製造方法

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EP2540845A4 EP2540845A4 (de) 2016-03-09

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US (1) US20120312432A1 (de)
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KR (1) KR101433493B1 (de)
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WO (1) WO2011105609A1 (de)

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JP6537131B2 (ja) * 2015-02-20 2019-07-03 公立大学法人兵庫県立大学 鉄板およびその製造方法
US10594172B2 (en) * 2015-11-12 2020-03-17 Hamilton Sundstrand Corporation Electric component including custom metal grain orientation
JP6156613B1 (ja) 2015-12-11 2017-07-05 新日鐵住金株式会社 成形品の製造方法、及び成形品
JP6669052B2 (ja) * 2016-11-30 2020-03-18 日本製鉄株式会社 変圧器、変圧器用の板状鉄心及び変圧器用の板状鉄心の製造方法
JP7010358B2 (ja) * 2018-02-16 2022-01-26 日本製鉄株式会社 無方向性電磁鋼板、及び無方向性電磁鋼板の製造方法
WO2023112891A1 (ja) * 2021-12-16 2023-06-22 Ｊｆｅスチール株式会社 無方向性電磁鋼板およびその製造方法
JP7439993B2 (ja) * 2021-12-16 2024-02-28 Ｊｆｅスチール株式会社 無方向性電磁鋼板およびその製造方法

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JP5492975B2 (ja) 2014-05-14
KR101433493B1 (ko) 2014-08-22
CN102869795A (zh) 2013-01-09
CN102869795B (zh) 2015-07-08
EP2540845A4 (de) 2016-03-09
US20120312432A1 (en) 2012-12-13
KR20120127652A (ko) 2012-11-22
JPWO2011105609A1 (ja) 2013-06-20
WO2011105609A1 (ja) 2011-09-01

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