CN102869795B - Metallic material which is solid solution of body-centered cubic (bcc) structure having controlled crystal axis <001> orientation, and process for producing same - Google Patents

Metallic material which is solid solution of body-centered cubic (bcc) structure having controlled crystal axis <001> orientation, and process for producing same Download PDF

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CN102869795B
CN102869795B CN201180016355.4A CN201180016355A CN102869795B CN 102869795 B CN102869795 B CN 102869795B CN 201180016355 A CN201180016355 A CN 201180016355A CN 102869795 B CN102869795 B CN 102869795B
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bcc
metallic substance
deformation
centered cubic
solid solution
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CN102869795A (en
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福富洋志
冈安和人
小贯祐介
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YOKOKAMA STATE UNIV
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
    • 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
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Materials Engineering (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Soft Magnetic Materials (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Abstract

Provided are a metallic material, e.g., an electromagnetic material (magnetic steel sheet), that has a processed surface along which crystal axes <001> of the metallic material have been distributed by controlling the distribution of the crystal axes <001>, and a process for producing the metallic material. The metallic material, which is, for example, an electromagnetic material (magnetic steel sheet), is obtained by subjecting a metallic material comprising a solid solution of a body-centered cubic (BCC) structure to hot compression at a temperature within a range where the solid solution is constituted only of a BCC phase, thereby distributing crystal axes <001> of the metal along the processed surface of the metallic material. The process is characterized by: heating the metallic material which is, for example, an Fe-Si alloy to a temperature in a range where the alloy is a solid solution constituted only of a BCC phase; and compressing this BCC-phase solid solution at a straining rate at which the solute atom atmosphere appearing in the BCC-phase solid solution governs movements for dislocation and at which grain boundaries are kept movable using, as a power therefor, strain energy that has accumulated in the grains, thereby distributing {100} planes in parallel to the processed surface.

Description

As metallic substance and the manufacture method thereof of the sosoloid of orientation controlled body-centered cubic (BCC) structure of crystallographic axis < 001 >
Technical field
The orientation that the present invention relates to as crystallographic axis <001> is controlled in metallic substance and the manufacture method thereof of the sosoloid of body-centered cubic (BCC) structure in plate face, the electromagnetic material that the core material of such as electric installation uses and manufacture method thereof.
Background technology
As the example by making the crystallographic axis of metal unanimously obtain large technique effect, there is widely used electro-magnetic steel plate in the electrical apparatus.Such as, in the determined situation of the magnetic field orientation that the transformer shown in Fig. 3 is such, use the controlled grain-oriented magnetic steel sheet of crystallographic axis.In figure 3, dotted line 33 represents the flowing of magnetic line of force, and wishes that the easy direction of magnetization of core material 31 is in the face of stacked sheet material.
In addition, in the rotor and stator of electric motor, in order to reduce iron loss, so-called non-oriented electromagnetic steel sheet having is used.Such as, as shown in Figure 4, single-phase SRM(switched reluctance motor (Switched reluctancemotor)), by be wound with the coil be connected with external power source stator 10, can be rotatably set in stator 10 inside and when supplying external power source to stator 10, being interacted by electromagnetic force with this stator 10 and carrying out rotating rotor 20 is formed.
Stator 10 comprises: there is the yoke 12 of ring type structure, from yoke 12 towards rotor 20 along radial direction projecting and in circumferential direction through regulation the mutually isolated multiple magnetic poles 16 of notch 14, be wrapped in the coil 18 be connected these magnetic poles 16 and with external power source.
The stator 10 of electric motor manufactures by the following method, from very thin electro-magnetic steel plate, goes out the stator piece of the planeform with yoke 12 and magnetic pole 16, the stator piece prepared like this is laminated into certain height and makes iron core, winding around 18 on this iron core.
In such electric motor, with the rotation of its rotor, field direction changes centered by the turning axle of rotor.Therefore, as the electro-magnetic steel plate of stator and rotor, so-called direction-free electro-magnetic steel plate (for example, referring to patent documentation 1) is used.
The anisotropy that crystallographic axis causes is there is in the magnetization of steel, <001> the most easily magnetizes and hysteresis loss is few, secondly, <011> easily magnetizes and hysteresis loss is few, be difficult to most magnetize and hysteresis loss large for <111>.Therefore, it is desirable that in the stator and rotor of electric motor, make <001> preferentially in radial direction orientation, easily carrying out magnetized while, reduce the iron loss that hysteresis loss causes.That is, it is desirable that <001> is centered by the axle of electric motor, the symmetrically core material of orientation.
But, because the <001> also not controlling now steel plate fully makes it the technology of orientation, therefore, as secondary kind plan, to avoid <111> in the orientation of radial direction, and avoid <001> be partial to steel plate specific direction be oriented to object, by Nippon Steel (strain), JFE iron and steel (strain) etc. develop as shown in Figure 5 there is no stereochemical orientation completely and the non-oriented electromagnetic steel sheet having be made up of silicon steel, for reality.Such as to be called that the trade(brand)name of Ha イ ラ イ ト コ ア, ホ ー system コ ア (being all registered trademark) is sold from Nippon Steel (strain).
But, do not having in the non-oriented electromagnetic steel sheet having of three-dimensional specific orientation shown in Fig. 5, although easily direction of magnetization is not partial to the specific direction of steel plate, but the <001> as the easy magnetizing axis of crystallization is mostly not along steel plate surface, the magneticflux-density along steel plate surface therefore can not be improved.Therefore, in the efficiency raising of electric motor, limitation is had.
Therefore, consider from the energy-conservation viewpoint of electric motor, wish to develop following non-oriented electromagnetic steel sheet having, namely as shown in Figure 6, { 100} is parallel relative to steel plate surface for crystal plane, and as the <001> of the easy magnetizing axis of crystallization along steel plate surface and in 360 degree of even orientations in direction in the face of steel plate, thus improve the non-oriented electromagnetic steel sheet having (for example, referring to non-patent literature 1) of the magneticflux-density along electro-magnetic steel plate face.
In addition, in order to improve the efficiency of transformer, it is desirable to develop the grain-oriented magnetic steel sheet in the direction of passage <001> orientation of magnetic line of force.
Therefore, in order to improve the efficiency of the electromagnetic equipment such as electric motor and transformer, wish the crystallographic axis <001> controlling electromagnetic material.
Prior art document
Patent documentation
Patent documentation 1: JP 2006-87289 publication
Non-patent literature
Non-patent literature 1:NIPPON STEEL MONTHLY 20054.P11-14
Summary of the invention
Invent problem to be solved
At present, because of 011}(compressing surface) and the growth of fiber texture, in the metal of the known face-centered cubic such at Al (FCC) structure, realize the crystalline orientation having rotational symmetry around compressional axis, uniaxial compression processing is effective.In addition, for the metal of such body-centered cubic (BCC) structure of Fe, known to uniaxial compression processing (cold reduction) under normal temperature, { the duplex-fiber texture of 111}+{100}, namely { 111} is with { the Rotational Symmetry orientation that 100} is parallel with compressing surface is formed as the crystalline orientation for stabilization.
But, there are the following problems, namely, in the existing uniaxial compression for Fe is processed, the orientation not only bringing the <001> with excellent magnetic properties parallel with steel plate surface 100}, and also can not make <001> in plate face orientation { 111} also exists jointly.In addition, in existing uniaxial compression processing, produce in plate face the state that 111} mono-side grows up more, therefore, present situation is, uniaxial compression processing can not be utilized as making the manufacturing technology of <001> electro-magnetic steel plate of orientation in plate face.
At present, not only uniaxial compression processing, and also other working method is also difficult to the orientation controlling easy magnetizing axis <001>.Therefore, can say and to control in the mode that easy magnetizing axis <001> is parallel with the surface of steel plate, the manufacture method obtaining the non-oriented electromagnetic steel sheet having of the having excellent magnetic properties that magneticflux-density is high, iron loss is low does not exist.That is, the non-oriented electromagnetic steel sheet having of easy magnetizing axis <001> orientation in plate face does not exist.
Therefore, the present invention in view of above-mentioned present situation, to control the crystallographic axis of metal for problem.Such as, with by the easy magnetizing axis <001> of iron material control for along machined surface for problem.And, with by easy magnetizing axis <001> is controlled as along machined surface, there is provided a kind of magnetization along plate face easily and high magneticflux-density can be obtained, and iron loss is low, the metallic substance of having excellent magnetic properties and manufacture method thereof be as problem.
For solving the means of problem
All the time, there will be a known when at high temperature uniaxial compression distortion being carried out to the Al-Mg solid solution alloy of FCC structure, formed and comprise 110}(compressing surface) and the technology of crystalline orientation.But the present inventor carries out for obtaining that { found that of the research of 100}, when increasing deflection, { the increase Growing of 100} and deformation soon, only becomes { the crystalline orientation of 100} existence.
The result experimentally carrying out studying for its mechanism finds, the change of this orientation is, when the amount of the dislocation due to distortion increases, { crystal grain in 100} orientation consumes because crystal boundary moves so that { crystal grain of other crystal orientation headed by 110} orientation is also preferentially grown up and produced.
And be conceived to following situation, that is, consider that the import volume of the dislocation of Accompanying Deformation is few, { 100} is the crystal orientation that the summation index of shear deformation amount in crystallization and Taylor (Taylor) factor are little, and { 100} is stable relative to distortion.
In addition, in fine aluminium (Al), do not find that { 110} is to { the change of 100} from this, therefore, infer the distortion with compression in Al-Mg alloy, produce when to pull (drawing I ず Ru) be overriding deformation mechanism as the dislocation motion of magnesium (Mg) the atmosphere gas of solute atoms, propose being uniformly distributed of dislocation and bring that { crystal boundary in 100} orientation moves the hypothesis of priority.
According to this hypothesis, contriver thinks, even the sosoloid of body-centered cubic (BCC) structure, also produces the crystalline orientation different from pure metal.And, be conceived in the uniaxial compression distortion of BCC metal, because slip is different compared with FCC, at room temperature also different from FCC, form { 100} and the { state that 111} exists jointly, and { { Taylor factor of 111} is low for the Taylor factor ratio of 100}.
Therefore, following conception is obtained, namely, as long as the dislocation motion pulling solute atoms atmosphere gas can be found to become the deformation mechanism of domination, and the processing conditions of crystal boundary movement can be carried out, just { 111} can be cut down, on the other hand, { 100} frequent ground is along the technology of the material of plate planar orientation to develop manufacture.
Estimate the metallic substance that this conception is generally applicable to body-centered cubic (BCC) structure.Therefore, as the metallic substance effectively utilizing this conception, to the iron-silicon alloy with body-centered cubic (BCC) structure, namely silicon steel is studied, found that, in order to increase magneticflux-density, available processing conditions controls the <001> orientation in the coarsening of necessary crystallization particle diameter and plate face.
Based on this discovery, specify that the manufacture method combination cold working relative to existing non-oriented electromagnetic steel sheet having and thermal treatment, or hot-work and thermal treatment these two process, only with hot uniaxial compression processing or such a process of hot plane deformation compression process, just can manufacture easy magnetizing axis <001> and be controlled as electro-magnetic steel plate along machined surface, thus complete the present invention.
A first aspect of the present invention provides a kind of manufacture method of metallic substance, it manufactures the manufacture method as the metallic substance of the sosoloid of body-centered cubic (BCC) structure, it is characterized in that, described metallic substance, by processing in the thermo compression of the temperature province becoming BCC single phase solid solution, makes crystallographic axis < 001 > of described metallic substance distribute along the machined surface of described metallic substance.
The present invention just can make the crystallographic axis <001> of metal distribute along machined surface because not needing the thermal treatment after processing, its principle can be applied in the metallic substance of the sosoloid as body-centered cubic (BCC) structure, and therefore it is applied widely.
In addition, a second aspect of the present invention is the manufacture method of a kind of metallic substance, such as electro-magnetic steel plate, it is characterized in that, described metallic substance is Fe-Si alloy, this alloy is being become the temperature province heating of BCC single phase solid solution, so that the motion that the solute atoms atmosphere gas occurred in this BCC single phase solid solution props up misfit dislocation can be maintained, and crystal grain boundary can be accumulated in the speed of deformation of the machining state of the deformation energy movement as motivating force in crystal grain, compression process is carried out to described BCC sosoloid, thus, { 100 } distribution parallel with machined surface is made.
So that the motion that the solute atoms atmosphere gas occurred in BCC single phase solid solution props up misfit dislocation can be maintained, and crystal grain boundary can be accumulated in the speed of deformation of the machining state of the deformation energy movement as motivating force in crystal grain, when compression process is carried out to BCC single phase solid solution, { 100 } distribution parallel with machined surface can be made.That is, <001> distributes along machined surface.
In addition, a third aspect of the present invention is the manufacture method of the metallic substance described in first aspect or second aspect, such as electro-magnetic steel plate, it is characterized in that, the sosoloid of described body-centered cubic (BCC) structure is Fe-Si alloy, by described Fe-Si alloy becoming the temperature province heating of BCC single phase solid solution, be 1 × 10 in speed of deformation -5s -1~ 1 × 10 -1s -1scope in carry out compression process.
When sosoloid is Fe-Si alloy, the motion that the solute atoms atmosphere gas occurred in BCC single phase solid solution props up misfit dislocation can be maintained, and crystal grain boundary can be accumulated in the speed of deformation of the machining state of the deformation energy movement as motivating force in crystal grain for 1 × 10 -5s -1~ 1 × 10 -1s -1scope in, when carrying out the compression process under this state, { 100 } distribution parallel with machined surface can be made.Such as, be 1 × 10 in speed of deformation -5s -1~ 1 × 10 -1s -1scope in carry out uniaxial compression and add man-hour, can the electro-magnetic steel plate of the good Fe-Si alloy of acquired character.At this, it is desirable that Fe-Si alloy be in % by weight containing 1 ~ 7% Si, remainder is the Fe-Si alloy of Fe and inevitable impurity.
In addition, the invention described in fourth aspect present invention is the metallic substance described in the third aspect, specifically, it is characterized in that, in the manufacture method of electro-magnetic steel plate, described temperature province is the temperature within the scope of 800 ~ 1300 DEG C.
By temperature range being limited, the electro-magnetic steel plate that reproducibility is good, characteristic is good can be manufactured.
In addition, invention described in fifth aspect present invention is the metallic substance described in fourth aspect, specifically, it is characterized in that, in the manufacture method of electro-magnetic steel plate, by described compression process, it is the deformation of-0.5 that the single phase solid solution to described body-centered cubic (BCC) structure gives at least total deformation quantity.
Processed by uniaxial compression, applying at least total deformation quantity is the deformation of-0.5, thereby, it is possible to positively obtain electro-magnetic steel plate <001> being controlled the high-quality in plate face.The low crystal orientation of deformation energy in uniaxial compression distortion be 100}(compressing surface), in addition, because this orientation is stable relative to being out of shape, in distortion, crystal boundary moves and makes this crystal grain become large, as long as so increase deformation quantity, { 100} fiber texture will be grown up.Deformation more can obtain good result more greatly.Adopt and increase the method for total deformation quantity, parallel with machined surface { growth of 100} is remarkable.
In addition, the present invention is a kind of metallic substance, and it is the metallic substance of the sosoloid as body-centered cubic (BCC) structure, it is characterized in that, is processed by thermo compression, and crystallographic axis <001> distributes along machined surface.Especially, in the metallic substance be made up of the sosoloid of body-centered cubic (BCC) structure, represent the φ of the crystal orientation distribution function (ODF) of the distribution of crystallographic axis < 001 > of the metal along machined surface 2orientation density on the Φ=0 ° line in=0 ° of cross section is more than 14 times relative to mean value 1.
By the present invention, achieve the high concentration of the unavailable Orientation density towards specific direction at present.
In the metallic substance of the sosoloid as body-centered cubic (BCC) structure, in hot uniaxial compression processing under the state that solute atoms atmosphere gas drag motion becomes overriding deformation mechanism, dislocation in sosoloid similarly distributes, therefore, according to dislocation deformation energy distribution and cause crystal boundary to move.So, the little { state of 100} growth parallel with plate face of deformation energy is formed.Further, when carrying out hot rolling or hot plane deformation compression process, <001> is towards prolonging direction.That is, under any circumstance all being controlled by <001> is along machined surface.
The sosoloid of described body-centered cubic (BCC) structure is the metallic substance of Fe-Si alloy, specifically, in the hot uniaxial compression processing of electro-magnetic steel plate, also easily can realize the φ of the crystal orientation distribution function (ODF) of the distribution investigating < 001 > 2orientation density on the Φ=0 ° line in=0 ° of cross section is the electro-magnetic steel plate of more than 14 times relative to mean value 1.
In existing sheet material, the φ of crystal orientation distribution function (ODF) 2orientation density on the Φ=0 ° line in=0 ° of cross section is less than 2 relative to mean value 1.
Control the electro-magnetic steel plate of the Fe-Si alloy that the distribution of 001} makes itself and machined surface parallel compared with existing non-oriented electromagnetic steel sheet having, its excellent.
Invention effect
According to metallic substance of the present invention and manufacture method thereof, the controlled metallic substance of its crystallographic axis can be obtained, especially, for electro-magnetic steel plate, the easy magnetizing axis <001> of iron can be provided to be controlled as along the high and electro-magnetic steel plate of the having excellent magnetic properties that iron loss is low of machined surface, magneticflux-density.
Accompanying drawing explanation
Fig. 1 is the φ of the crystal orientation distribution function (ODF) of the non-oriented electromagnetic steel sheet having that the manufacture method of the hot uniaxial compression processing of the application of the invention manufactures 2=0 ° of sectional view;
Fig. 2 is the φ of the crystal orientation distribution function (ODF) of existing non-oriented electromagnetic steel sheet having 2the sectional view of=0 °;
Fig. 3 is the figure of the flowing of the magnetic line of force illustrated in the electro-magnetic steel plate of transformer;
Fig. 4 is the pie graph of the electric motor using electro-magnetic steel plate;
Fig. 5 is the sketch chart of the crystallization distribution representing existing so-called non-oriented electromagnetic steel sheet having;
Fig. 6 is the sketch chart of the crystallization distribution representing the non-oriented electromagnetic steel sheet having manufactured by manufacture method of the present invention;
Fig. 7 is the figure that the situation that uniaxial compression is processed is described, before (a) compression, after (b) compression;
Fig. 8 illustrates the figure carrying out the situation of plane deformation compression process, (a) (b) clamp for machining, the sample before (c) processing, the sample after (d) processing;
Fig. 9 is the figure that rolling processing is described;
Figure 10 is the figure that multidirectional rolling processing is described;
Figure 11 is the sectional view that drawing-die processing is described;
Figure 12 is the model diagram of body-centered cubic (BCC) structure;
Figure 13 is the figure of the situation in the easy magnetizing axis <001> orientation represented in the stator of electric motor, (A) existing non-oriented electromagnetic steel sheet having, the electro-magnetic steel plate that (B) is desirable;
Figure 14 is { figure of 100} pole graph, (A) existing non-oriented electromagnetic steel sheet having, the electro-magnetic steel plate that (B) the present invention relates to that represent in the stator of electric motor;
Figure 15 is the figure of the magnetic properties of electro-magnetic steel plate (solid line) representing existing non-oriented electromagnetic steel sheet having (dotted line) and the present invention relates to.
Embodiment
Below, the embodiment of electro-magnetic steel plate of the present invention and manufacture method thereof is described.
When at high temperature making deform metallic material, various mechanism contributes to distortion.Generally speaking, being undertaken being out of shape by the motion of dislocation in metallic substance is basic mechanism.
One of phenomenon of domination dislocation motion is the combination of temperature by certain scope and speed of deformation, the drag motion of the solute atoms atmosphere gas occurred in solid solution alloy.This motion is called that dislocation is surrounded the state of carrying out moving by solute atoms.Such as, in Fe-Si alloy, the Si as solute atoms forms the solute atoms atmosphere gas existed around dislocation, under the texturizing condition of certain scope with the concentration higher than the mean concns of crystallization entirety, dislocation can not go out from the qi exhaustion of solute atoms atmosphere, pulls dislocation and moves.So, dislocation is because pulling solute atoms atmosphere gas, and its movement velocity reduces.Consequently, this dislocation is different from the distortion near normal temperature, becomes and is uniformly distributed in crystallization.That is, carry out the dislocation of the drag motion of solute atoms atmosphere gas, easily become and be uniformly distributed in crystallization.
At this, dislocation is lattice imperfection, has deformation energy.The amount contributing to the dislocation of being out of shape is different because of crystal orientation, therefore, even if give identical deflection, also different in the amount of each crystal grain Dislocations, and consequently, the deformation energy accumulated in each crystal grain is different.But under common processing conditions, dislocation distributes in the mode of the energy of deformation that cancels each other out, therefore, the difference of the dislocation desity of each crystal grain is not as the difference reflection of the deformation energy of original accumulation.
In contrast, as the texturizing condition in the present invention, produce in the compression process that pulls under the high temperature of the dislocation motion of solute atoms atmosphere gas, dislocation is uniformly distributed, therefore, the cancel each other out effect of deformation of dislocation is little, and the amount difference of dislocation is reflected as the difference of the deformation energy of original accumulation.
Like this, when solute atoms atmosphere gas domination dislocation motion, the amount of the deformation energy that each crystal grain possesses depends on crystal orientation consumingly.So the crystal grain that deformation energy is little becomes large, and the crystal grain boundary of the crystal grain that deformation energy is little preferentially moves.
The crystal orientation that deformation energy is low, the sosoloid of body-centered cubic (BCC) structure uniaxial compression distortion in be 100}(plate face), in the plane deformation compression sets such as rolling be 100}(plate face), <001>(prolonging direction).Therefore, the crystal grain of these crystal orientations consumes the crystal grain of other crystal orientation and grows up.
In addition, because { orientation of 100} is stable for distortion in compression set, therefore, in distortion, crystal boundary carries out moving makes this crystal grain become large, therefore, as long as increase deformation quantity, in uniaxial compression distortion, { 100} fiber texture is grown up, and in plane deformation compression set, { 100}<001> texture is grown up.
At this, { 100} represents machined surface, and <001> represents bearing of trend.
The present invention completes based on above-mentioned opinion, and in the method for the invention, in arbitrary distortion of uniaxial compression distortion, plane deformation compression set, { 100} is parallel-oriented with plate face.In compression set, crystal plane { 100} and plate face orientation abreast, especially in uniaxial compression processing, so that as crystal plane, { <100> of the normal of 100} is for turning axle, in the direction at a right angle relative to the compression direction in plate face, crystallization direction <001> at 360 degree evenly and distribute thick and fast.In addition, in the distortion of the plane deformations such as rolling, when the thickness of sheet material reduces because of compression process, sheet material extends to a direction.In this situation, <001> is in prolonging direction dense distribution.
When the electro-magnetic steel plate that the surface manufacturing easy magnetizing axis <001> and steel plate distributes abreast, for Fe-Si alloy, at least will contain Si, and the alloy that remainder comprises Fe and inevitable impurity is becoming the temperature province heating of body-centered cubic (BCC) structure sosoloid, in this condition, overriding deformation mechanism is become with the motion that can maintain the dislocation pulling the solute atoms atmosphere gas produced in described BCC sosoloid, and, the Deformation velocity of the machining state of deformation energy movement as motivating force that crystal grain boundary can be accumulated in crystal grain, the plane deformation compression process such as uniaxial compression processing or rolling are carried out to the sosoloid of described body-centered cubic (BCC) structure, by this processing, make that { 100} and machined surface distribute abreast to high-density.
And, determine the temperature of processing conditions and speed of deformation, for the temperature of temperature province within the scope of 800 ~ 1300 DEG C and speed of deformation are 1 × 10 -5s -1~ 1 × 10 -1s -1speed of deformation in scope.
The total being put on the deformation quantity on the sosoloid of body-centered cubic (BCC) structure by compression process is counted more than-0.5 with true deformation.As the state of target, grow up monotonously together with the increase of deformation quantity, when deformation quantity is few, become insufficient grow states, as long as but deflection increases the state just forming excellence, therefore, the deformation quantity applied does not have the upper limit, and, also can apply deformation several times.
In addition, when being described composition, the Si in the sosoloid of body-centered cubic (BCC) structure is in order to make the intrinsic resistance of steel plate increase and make eddy current reduce, improve the core loss value caused by eddy current and add.Body-centered cubic (BCC), as long as the sosoloid BCC of structure is single-phase, can not be the alloy of two component system, also can be more than the ternary also containing the composition beyond Si be.When the sosoloid of body-centered cubic (BCC) structure is Fe-S i alloy, Si content is the compositing range of 1 ~ 7 % by weight degree.S i containing quantity not sufficient 1 % by weight time, can not fully obtain low iron loss need intrinsic resistance, when its content is more than 7 % by weight, when compressing, crackle significantly increases, and compression process becomes difficulty, so, lower limit set is preferably 1 % by weight by Si content, and the upper limit is set as 7 % by weight.
As the inevitable impurity of Fe-Si alloy, can enumerate: C, Mn, P, S, Al, N etc., but especially for S-phase mutual reactance and separate out fine sulfide M nS and make magnetic properties significantly deterioration Mn and hinder processibility P for, be preferably set to less than 0.01 % by weight, for hindering the S of crystal grain-growth, be preferably set to less than 0.0001 % by weight.
When the sosoloid of body-centered cubic (BCC) structure is Fe-Si alloy, the temperature becoming the single-phase temperature province of BCC is set as to its temperature heated, is the temperature within the scope of 800 ~ 1300 DEG C.This is because, when S i content is in the scope of 2 ~ 5 % by weight, the Fe-Si alloy always as BCC from low temperature to fusing point, when Si contains quantity not sufficient 2 % by weight, depend on its content, at high temperature once become FCC, just likely hinder { the formation of 100} fiber texture.Therefore, as the temperature province containing quantity not sufficient 2 % by weight containing Si, as the temperature becoming the single-phase temperature province of BCC, the low temperature side in the temperature range of 800 ~ 1300 DEG C is heated.
The speed of deformation during compression process of BCC single phase solid solution, represents time per unit gives how much deformation, is so-called process velocity.Fast or slow with process velocity, change the mechanism that domination contributes to the dislocation motion of being out of shape.Therefore, under the state that the sosoloid of body-centered cubic (BCC) structure is heated to the temperature becoming the single-phase temperature province of BCC, process velocity is restricted to the speed that the solute atoms atmosphere gas that can keep occurring in BCC sosoloid props up the processing conditions of the motion of misfit dislocation.The speed of deformation when sosoloid of body-centered cubic (BCC) structure is Fe-Si alloy, by the combination with the temperature in 800 ~ 1300 DEG C of temperature ranges, 1 × 10 -5s -1~ 1 × 10 -1s -1setting in scope.
Confirm for the Fe-Si alloy that S i content is 3 % by weight, when temperature 900 DEG C, speed of deformation is 1 × 10 -5s -1~ 5 × 10 -2s -1scope, when temperature 1250 DEG C, speed of deformation is 1 × 10 -4s -1~ 1 × 10 -2s -1scope.Consequently, based on the condition for obtaining same orientation while content increase, if speed of deformation is identical, then change to low temperature side, when making content increase and be set as certain by temperature, for the hypothesis that the process velocity obtaining same orientation increases, as the scope by deciding this speed of deformation with the Si content in above-mentioned scope and the speed of deformation of processing with the uniaxial compression combinationally used of temperature and putting on Fe-Si alloy.
< embodiment >
As the sosoloid of body-centered cubic (BCC) structure of material, by thickness 20mm, width 140mm, the plate of length 290mm, the diameter 12mm utilizing electric discharge machining apparatus to make, the cross section of height 18mm size is the steel disc of circular column, described plate is that the steel ingot of the 40kg made carrying out vacuum melting carries out the hot rolling (Heating temperature 1100 DEG C × 60 minutes that final thickness is 40mm, final rolling temperature more than 850 DEG C), after being cut into length 320mm, carry out the hot rolling (Heating temperature 1100 DEG C × 60 points that final thickness is 20mm again, final rolling temperature more than 850 DEG C), then, the steel plate cut-out obtained like this is made.
In addition, steel ingot is for be set as 1.5,3,4,5 % by weight by Si, inevitable impurity Mn and P is set as be set as less than 0.01 % by weight, by S making less than 0.001 % by weight, but in four kinds of materials A, B, C and D, as understood in the analytical value after the making shown in from following table 1, except Mn, P, S, contain C, Al, N etc. of % by weight shown in table as inevitable impurity.
［ table 1 ］
With process furnace by each steel disc of above-mentioned composition under 900 DEG C or 1250 DEG C carry out heating condition, with 1 × 10 -5s -1~ 5 × 10 -2s -1speed of deformation in scope, until true shape becomes-1.0, is processed as diameter 20mm, height 6.6mm respectively by uniaxial compression, carries out slow cooling, obtain steel plate respectively in normal temperature air.
In uniaxial compression processing, use the function that the pinblock speed of the tensile testing machine (Shimadzu オ mono-ト グ ラ Off) of the loading capacity shown in Fig. 72 tons is certain.When carrying out compression process with tensile testing machine, columned compression clamp is being installed up and down, is putting into the steel disc as sample betwixt, from applying power up and down, in order to temperature be remained on necessarily in compression process, upper and lower compressed rod and steel disc entirety are put into process furnace.In the figure 7, heat source model is recorded.
In obtained steel plate, will by with temperature 900 DEG C, speed of deformation 5.0 × 10 -5s -1the electro-magnetic steel plate of the material B manufacture of the Si content 3 % by weight of processing is divided into two portions, make highly to become 1/2nd, make the mensuration sample of the circular plate shape of diameter 20mm × 3.3mm, with the face cut off for object, after opposite is ground, with being called that the X-ray diffraction method of Schul z reflection method measures the azimuth distribution of crystallization, obtain crystal orientation distribution function (ODF).Specifically, by Schulz reflection method, { 100} pole graph, { 110} pole graph, { 211} pole graph, crystal orientation distribution function (ODF) that with computer calculate, three pole graphs can be described reconcilably, that represent three-dimensional crystals azimuth distribution is described by the data measuring acquisition respectively.
Fig. 1 is the φ of the ODF obtained so that the mode of three pole graphs can be illustrated reconcilably to carry out computer calculate 2=0 ° of sectional view.In same figure, φ 1, Φ, φ 2for Eulerian angles, the level line along the bottom and upper segment of tetragon represents the distribution of the crystal orientation density in steel plate surface.Isocontour numeric representation, with the Orientation density represented relative to the multiple of mean value 1, in same figure, between numerical value 20 and the level line of 1, describes the level line of numerical value 18,16,14,12,10,8,6,4 successively.On the line of the known upper ledge at Fig. 1 and Φ=0 °, even also see the high gathering more than 14 times in minimum region, form sharp-pointed { 100} fiber texture.This value is the value of the excellence of the value considerably beyond the existing non-oriented electromagnetic steel sheet having shown in Fig. 2.
Fig. 2 is the φ of the non-oriented electromagnetic steel sheet having used in a large number as existing non-oriented electromagnetic steel sheet having obtained by existing method 2=0 ° of sectional view, the known Orientation density along top is 0.5 ~ 2.0, and is substantially untextured state.
In addition, in an embodiment, the crystal orientation distribution of the material before processing is not mentioned, this is because what kind of state is the state before no matter processing be, as long as increase deformation quantity, { 100} and parallel-oriented { the 100} fiber texture of machined surface just can be formed by thermo compression processing.Certainly, the material that the crystal orientation same with existing non-oriented electromagnetic steel sheet having distributes can also be prepared to have.In addition, in the above-described embodiment, the cross section of material is circular, but also can be plate or the cylinder in the square or polygonal cross section outside circle.In addition, according to same reason, the face of applying uniaxial compression processing also can be the arbitrary shape outside plane.
At this, the situation of the easy direction of magnetization of the electric motor of the main application as electro-magnetic steel plate is described particularly.Discoideus stator material goes out centre portions and groove uses.Therefore, as stator material, the importance of the magnetic pole 16 of Fig. 4.
Figure 12 represents the model of BCC structure.BCC structure has symmetry up and down, and therefore, [100], [010] represented by this figure, [001] are of equal value, and this three root knots crystallographic axis general name is expressed as <001>.In addition, cubical is all of equal value, therefore, be generically and collectively referred to as face { 001}, { 100}, { 010} represents identical content.
Below, Figure 13 (A) represents the situation of the easy magnetization axis of the existing non-oriented electromagnetic steel sheet having of the stator of electric motor.In existing electro-magnetic steel plate, easy magnetization axis is three-dimensionally towards all directions of 360 degree.In addition, in Figure 13 (B), represent the easy magnetization axis in the electro-magnetic steel plate of approximate desired.
In addition, Figure 14 represents the { distribution situation of the <001> of the easy magnetization axis of 100} pole graph.Figure 14 (A) is the distribution situation of existing non-oriented electromagnetic steel sheet having, and Figure 14 (B) is the distribution situation of the <001> of the electro-magnetic steel plate that the present invention relates to.The degree that the density of the numeral <001> in figure is concentrated relative to mean value 1.
In existing non-oriented electromagnetic steel sheet having, the minimum value giving the peripheral part of the large impact of characteristic is less than 0.8 times of mean value.On the other hand, when observing the pole graph of the electro-magnetic steel plate of this exploitation shown in Figure 14 (B), the minimum value of peripheral part is more than 1.6 times of mean value, central part exceedes 19 times of mean value, therefore, the existing material of the <001> density ratio prior art of known important peripheral part is large and high.
Figure 15 represents the magnetic properties of electro-magnetic steel plate of the present invention.Dotted line in figure is the magnetic properties of existing non-oriented electromagnetic steel sheet having, and solid line is the magnetic properties of electro-magnetic steel plate of the present invention.Obviously, for the magnetic field applied, can expect to obtain large magneticflux-density, and the characteristic being related to the electromagnetic equipment of electric motor etc. is improved.
In addition, in an embodiment, show the example single material being carried out to uniaxial compression processing, but consider batch production, also also can carry out compression process by stacked multiple material with the special compressor that loading capacity is large simultaneously, also can increase the size of material.
In addition, as the method for compression process, namely using the plane deformation compression process shown in Fig. 8, by meeting above-mentioned processing conditions, also can obtain { the parallel-oriented result of 100} and plate face.
In addition, in order to produce in batches, also can be the rolling processing shown in Fig. 9, in the rolling processing in the direction shown in Fig. 9, { 100} and rolling surface are grown up abreast, can obtain the sheet material that <001> is distributed in rolling direction mostly.In addition, add man-hour carrying out the multidirectional rolling shown in Figure 10, <001> multi-direction distribution in face can be made, obtain and process same effect with uniaxial compression.
In addition, as shown in figure 11, when heated condition makes parts by drawing-die, the metallic substance of wire can be obtained.The <001> of material is consistent with bearing of trend, therefore makes magnetic line of force by obtaining good characteristic during bearing of trend.
In addition, also can increase deformation quantity, make thinner electro-magnetic steel plate, so, the magnetic properties of the electro-magnetic steel plate obtained is more excellent, and this can understand from above-mentioned explanation.Because this processing is at high temperature implemented, therefore, lattice imperfection amount residual after processing is few, by processing the annealing of rear enforcement short period of time, can make the non-oriented electromagnetic steel sheet having reducing lattice imperfection amount further.
As embodiments of the invention, though adopt the Fe-S i as electromagnetic material, the present invention is applicable to the metallic substance that can carry out thermo compression processing under the state of body-centered cubic (BCC) structure.By application the present invention, { the metallic substance of 100} growth parallel with machined surface can be obtained by thermo compression processing.
Utilizability in industry
According to the present invention, the manufacture method of the controlled metallic substance in the orientation such as electromagnetic material of crystallographic axis is able to clearly, and by providing the electromagnetic material of good characteristic, electromagnetism loss of energy can be reduced, the cost being related to whole society reduces, and, also useful to environmental problem.
Nomenclature
The stator of 10 electric motor
12 yokes
14 notches
16 magnetic poles
18 coils
The rotor of 20 electric motor
31 magnetic cores
32 coils
33 magnetic line of force

Claims (7)

1. the manufacture method of a metallic substance, described metallic substance is the sosoloid of body-centered cubic (BCC) structure, it is characterized in that, by the temperature province of described metallic substance in the single phase solid solution becoming body-centered cubic (BCC) structure is heated, the motion of misfit dislocation is propped up with the solute atoms atmosphere gas that can maintain metallic substance described in described temperature province, and crystal grain boundary can be accumulated in the Deformation velocity of the machining state of the deformation energy movement as motivating force in crystal grain, thermo compression processing is carried out to described metallic substance, make the orientation of crystallographic axis < 001 > of described metallic substance along the plate face of described metallic substance and be uniformly distributed in 360 degree of directions in the face of plate.
2. the manufacture method of a metallic substance, it is characterized in that, described metallic substance is Fe-Si alloy, the temperature province of this alloy in the single phase solid solution becoming body-centered cubic (BCC) structure is heated, so that the motion that the solute atoms atmosphere gas occurred in the single phase solid solution of body-centered cubic (BCC) structure props up misfit dislocation can be maintained, and crystal grain boundary can be accumulated in the Deformation velocity of the machining state of the deformation energy movement as motivating force in crystal grain, thermo compression processing is carried out to the sosoloid of described body-centered cubic (BCC) structure, thus, make { 100} distribution parallel with machined surface.
3. the manufacture method of the metallic substance described in claim 1 or 2, it is characterized in that, the sosoloid of described body-centered cubic (BCC) structure is Fe-Si alloy, and described Fe-Si alloy is heated to the temperature province becoming single phase solid solution, is 1 × 10 in speed of deformation -5s -1~ 1 × 10 -1s -1scope in carry out thermo compression processing.
4. the manufacture method of metallic substance according to claim 3, is characterized in that, described temperature province is the temperature within the scope of 800 ~ 1300 DEG C.
5. the manufacture method of metallic substance according to claim 4, is characterized in that, is processed by described thermo compression, and it is the deformation of-0.5 that the single phase solid solution to described body-centered cubic (BCC) structure is given at least total deformation quantity of true deformation.
6. a metallic substance, it is the sosoloid of body-centered cubic (BCC) structure, it is characterized in that, thermo compression processing during manufacture by described metallic substance, defines the φ represented along the crystal orientation distribution function (ODF) of the distribution of crystallographic axis < 001 > of the metal in compression process face 2the Orientation density continuous print level line more than 1 in=0 ° of cross section is at φ 10 ° ~ 90 ° between along φ=0 ° with { the 100} fiber texture that exists in its vicinity of the line of 90 °.
7. metallic substance according to claim 6, is characterized in that, the sosoloid of described body-centered cubic (BCC) structure is Fe-Si alloy.
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