US20050258403A1

US20050258403A1 - Method of preparing polymer composite using unidirectionally solidified giant magnetostrictive material

Info

Publication number: US20050258403A1
Application number: US10/487,278
Authority: US
Inventors: Won Park; Zin Lee
Original assignee: Individual
Current assignee: Korea Advanced Institute of Science and Technology KAIST
Priority date: 2001-10-12
Filing date: 2002-09-13
Publication date: 2005-11-24
Also published as: WO2003032337A1; US7335317B2; EP1451834A1; DE60235717D1; EP1451834B1; KR20030030735A; JP2005505931A; KR100405960B1; US20060017039A1

Abstract

Disclosed is a preparation method of a polymer composite using a giant magnetostrictive material, which is advantageous in that electric resistivity and magnetostrictive strain are increased while the unidirectionally solidified texture in the material is maintained as it is. The method consists of removing the rare earth or the eutectic phase from a unidirectionally solidifed rare earth giant magnetostrictive material; and infiltrating a polymer resin to the rare earth or cutectic phase-removed void, followed by curing the infiltrated resin. Thereby, there can be provided the polymer composite, which is advantageous in that eddy current loss is decreased due to increased electric resistivity, and magnetostrictive strain is improved as well as fracture resistance is higher due to the soft and tough properties of polymer.

Description

TECHNICAL FIELD

The present invention pertains, in general, to methods of preparing a polymer composite using a giant magnetostrictive material, and more particularly, to a polymer composite having various improved properties, characterized in that the advantageous structure of the giant magnetostrictive material produced by unidirectional solidification can be maintained as it is by removing the rare earth phase or the eutectic phase from the magnetostrictive material and replacing the phase-removed void with a polymer resin.

PRIOR ART

In general, the term magnetostriction means that a material has various lengths in response to change of a magnetic field and, as its reverse reaction, a magnetization state of the material is altered in response to external mechanical strain. Compared to PZT piezoceramic materials and nickel based magnetostrictive materials conventionally used as transducers or actuator devices, rare earth (hereinafter, abbreviated to “RE”)-transition metal magnetostrictive materials are higher in magnetostrictive strain, with superior energy efficiency. Thus, the RE-transition metal magnetostrictive materials attain superiority over various application fields, and in particular, in the industrial fields related with aeronautics, communication, oil refining, automobiles, MEMS (micro electro mechanical system) and medicine. More specifically, such materials are used for high output actuators, linear and rotary motors, control of noise and vibration, pumps, fuel injection, robotics, position determination, valve actuations, micro positioning, sonar, audio systems, ultrasonic instruments, force sensing, endurance measurement, etc.
The RE-transition metal magnetostrictive material which is prepared by means of a unidirectional solidification is present in forms of a single crystal or aligned poly-grains. In order to obtain high magnetostrictive strain in such an alloy, grains in the alloy must be arranged in a specific direction. The reason is that upon unidirectional alignment of grains, the magnetostrictive strain is increased and internal loss generated at a grain boundary is also decreased. Such orientation in the magnetostrictive material is very important in the application fields to obtain high magnetostrictive strains at low magnetic field.
Among typical RE-transition metal magnetostrictive materials having aligned grains, there is highlighted an alloy comprising Tho_0.3Dy_0.7Fe_1.9. However, this alloy suffers from the disadvantages of short span life and difficult processing, due to high brittleness of a Laves phase (REFe₂phase, in which RE means a complete solid solution of Tb and Dy). With the aim of solving these problems, a larger amount of terbium (Th) and dysprosium (Dy) are added in order to form a larger amount of RE phase or the eutectic phase having superior ductility and toughness at boundaries of the Laves phase. As such, the RE phase or the eutectic phase comprises a densely formed network structure throughout the material.
As the phase diagram FIG. 4 shows, the eutectic phase comprises RE phase and REFe₂phase in a finely mixed state. When the total composition is very close to REFe₂there is just a little amount of the eutectic phase is formed, and in this case the REFe₂phase of the eutectic structure which forms at the eutectic temperature, crystallizes at the nearby existing primary REFe₂and only the RE phase is formed between large REFe₂primary dendrites. This type of eutectic solidification is called divorced eutectic solidification. However, if the total composition is closer to the exact eutectic composition, a larger amount of eutectic phase is formed in a regular type of finely mixed state.
The major disadvantage of the unidirectionally solidified RE-transition metal magnetostrictive material is its low electric resistance, attributable to the metal. Thus, since heat generation and energy loss are large due to eddy currents upon use of such a material in the ranges of high frequencies, the use of the above material is limited in the application fields requiring high frequency ranges.
Hence, there is used the method of reducing the eddy current loss by cutting the material to thin sheets (1 mm thickness) and layering them with insulator inbetween. But such layering process is difficult and expensive to perform because the RE-transition metal magnetostrictive material is hard and very fragile.
As an alternative, powders of the RE-transition metal magnetostrictive material are mixed with the polymer resin and prepared as a polymer composite, which is advantageous in terms of simple preparation process, low cost and easy compaction to various shapes. However, since small grains having magnetostrictive property are dispersed in a non-magnetic polymer matrix, the above composite is disadvantageous in light of inferior crystal orientation and low magnetization strength and thus much lower magnetostrictive strain, compared to the unidirectionally solidified material. Even so, more important advantages of the composite material are its good mechanical toughness and high electric resistance, due to the polymer matrix functioning as the insulator. By increasing the electric resistance, heat generation by eddy current is decreased and the usable frequency range is increased from several tens of kHz to several hundreds of kHz. In the case of preparing the composite by use of Tb_xDy_1-xFe_2-w, the total energy loss by eddy current is decreased to ⅙ level compared to unidirectionally solidified bodies. In addition, the composite has higher toughness under tensile stress.
Conventionally, the polymer composite is prepared as follows.

- (1) the cast RE-Fe magnetostrictive material ingot is pulverized under inert gas atmosphere to make grains;
- (2) the particles are mixed with a polymer binder and pores present therein are removed;
- (3) a mixture of the resin and the grains is compacted under pressure, provided that an external magnetic field of 100 Oe or more is vertically applied relative to a pressure axis to the grains for unidirectional alignment thereof upon compacting; and
- (4) the polymer resin is cured to produce the composite having excellent mechanical properties.

At present, the polymer composite is considerably lower in magnetostrictive strain than the unidirectionally solidified bodies, since the grains of the magnetostrictive material are very small and have poor crystal orientation. The reason why fine grains are low in magnetostrictive strain is that saturation magnetization strength of the surface is lower than that in the bulk, and as the distance between grains becomes longer, a coupling force therebetween is decreased. In particular, as in RE-iron magnetostrictive material, it is very important that the texture is maintained in the favorable crystal orientation, having a large magnetostriction.
Meanwhile, the RE-transition metal magnetostrictive material can be further increased in its magnetic properties through annealing. As for the RE-iron magnetostrictive material, the annealing process is performed at a temperature higher than 887° C., the eutectic temperature (see FIG. 4). In some cases, a magnetic field or compressive stress may be applied during annealing. However, such annealing process may cause the following problems, in which the RE phase or eutectic phase is melted at a temperature higher than the eutectic temperature and flows out of the material. In the RE phase-removed structure, the magnetic properties are improved but toughness of the material become much worse because the RE phase-removed portion forms a void, and the material is easily fractured. To prevent such phenomenon, the annealing process should be performed at a temperature lower than the eutectic temperature or the fraction of the RE phase should be decreased. However, the former case is disadvantageous because of a smaller heat treatment effect, and the latter case suffers from the drawback of low toughness.

DISCLOSURE OF THE INVENTION

Therefore, it is an object of the present invention to alleviate the problems in the prior art and to provide a method of preparing an aligned polymer composite, exhibiting excellent properties in high frequency ranges due to increased electric resistance and having high fracture resistance due to improved toughness of the material as well as improved magnetic properties, while a unidirectionally aligned texture of a unidirectionally solidified magnetostrictive material is maintained as it is.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 a is a view showing a schematic structure of a unidirectionally solidified giant magnetostrictive material, as a unidirectionally aligned composite comprising Laves (or REFe₂phase) and RE phase or eutectic phase;
FIG. 1 b is a view showing a void-formed structure after removal of a RE or eutectic phase from the structure shown in FIG. 1 a through annealing;
FIG. 1 c is a view showing a structure of the composite after infiltration of a polymer resin;
FIG. 2 a is an scanning electron microscopic photograph showing a RE phase-removed material having only a REFe₂phase;
FIG. 2 b is a photograph showing a structure of a cross-section of a polymer infiltrated composite, observed by an electron microscope;
FIG. 3 a is a photograph showing a structure of a unidirectionally solidified terphenol-D containing 80 vol % of a REFe₂phase, observed by an optical microscope;
FIG. 3 b is a photograph showing a structure of a polymer composite made of the material shown in FIG. 3 a, observed by an optical microscope;
FIG. 4 is a pseudobinary phase diagram of (Tb_0.3Dy_0.7)—Fe;
FIG. 5 is a graph comparing saturation magnetostriction of a conventional magnetostrictive material and a polymer composite by the present invention under various compressive stresses; and
FIG. 6 is compares the magnetostriction (λ) versus magnetic field (H) curves under a compressive stress of 7 MPa for the two materials of above FIG. 5.

BEST MODES FOR CARRYING OUT THE INVENTION

The present invention provides a method of preparing a polymer composite using a giant magnetostrictive material with a RE phase, comprising the steps of removing the RE phase from a unidirectionally solidified giant magnetostrictive material shown in FIG. 1 a and FIG. 1 b; and infiltrating a polymer resin to a RE phase-removed void, followed by curing the infiltrated resin (FIG. 1 c).
The polymer composite of the present invention is excellent in magnetostriction because a Laves phase comprising a texture formed by unidirectional solidification is maintained as it is, compared to conventional polymer composites containing the Laves phase of a powder form,.
In the giant magnetostrictive material usable in the present invention, a phase showing a giant magnetostriction phenomenon is contained, together with the RE phase. As the phase showing magnetostriction, use is preferably made of a rare earth-iron magnetostrictive material having grains aligned by unidirectional solidification, with excellent properties. Further, the iron element constituting the Laves phase may be alloyed with small amounts of other metals, for example, aluminum, manganese, cobalt and so on. In this regard, the rare earth-iron magnetostrictive material is exemplified by Tb_xDy_1-xFe_2-w(0.20≦x≦1.00, 0≦w≦0.20), Tb_xHo_1-xFe_2-w(0.10≦x≦1.00, 0≦w≦0.20), Sm_xDy_1-xFe_2-w(0.80≦x≦1.00, 0≦w≦0.20), Sm_xHo_1-xFe_2-w(0.60≦x≦1.00, 0≦w≦0.20), Tb_xHo_yDy₂Fe_2-w(0.10≦x≦1.00, 0≦y≦0.9, 0≦z≦0.8, 0≦w≦0.20, x+y+z=1), Sm_xHo_yDy_zFe_2-w(0.60≦x≦1.00, 0≦y≦0.4, 0≦z≦0.4, 0≦w≦0.20, x+y+z=1), etc. Of them, Tb_xDy_1-xFe_2-w(0.27≦x≦0.35) is preferably used in light of excellent magnetostrictive characteristics. More preferably, Tb_0.3Dy_0.7Fe_1.9(alias, known to “terfenol-D”) is used.
The giant magnetostrictive material having grains aligned by unidirectional solidification may be obtained by known methods (eg, Bridgman method, float zone melting, Czochralski method, etc.), which are apparent to those skilled in the art.
The RE phase or the eutectic phase is distributed between the primary REFe₂phases forming a network structure, the amount of which can be controlled by controlling the total composition of a giant magnetostrictive material. Removal of the RE phase can be achieved by thermally annealing the giant magnetostrictive material at a temperature higher than the eutectic temperature. Such annealing process functions to melt the eutectic structure containing the RE phase and causing it to flow out. At the same time, magnetic properties of the Laves phase are further increased by this annealing. The molten eutectic structure flows out of the material due to a high interfacial energy with the Laves phase. Since the Laves phase may coarsen during heat treatment but the unidirectionally aligned dendrite structure can be maintained as it is, the annealing process is very advantageous. The RE elements constituting the giant magnetostrictive material generally have a high tendency to oxidize, and thus the annealing process is preferably performed under inert gas or vacuum atmosphere.
In FIG. 2 a, it can be seen that the giant magnetostrictive material represented by Tb_xDy_1-xFe_2-wis annealed to remove the RE phase, whereby only REFe₂dendrite phase showing magnetic properties remains in the material structure. After the polymer resin is infiltrated to the material structure, the surface is polished. The polished structure is shown in FIG. 2 b. From this drawing, it can be seen that REFe₂phase is maintained as the aligned dendrite structure obtained from casting, while the RE or eutectic phase portion is replaced with the polymer resin.
The process of replacing the polymer resin to the RE phase-removed void in the structure of the magnetostrictive material is carried out by means of known methods, for example, infiltration. The polymer resin introduced into the material structure via infiltration is formed in a densely connected network structure in the material, thereby preventing propagation of cracks or absorbing fracture energy, thus providing high fracture resistance. In order that the polymer resin is completely filled into fine channels in the material, all gases present in the material should be removed under vacuum before the infiltration process is performed.
As the polymer resin applied to the infiltration process is preferably used a non-conductor to increase electric resistance. More preferably, with the aim of obtaining excellent wetting property between the polymer and the metal matrix and complete infiltration through fine channels, a polymer resin having low viscosity is used. The polymer resin may be suitably selected according to the properties required by those skilled in this art and is not specifically limited. Therefore, in the present invention, various polymer resins having different properties are applied and the giant magnetostrictive material combining various properties of polymers can be realized.
The polymer resin meeting the above requirements includes thermosetting resins or thermoplastic resins, which are exemplified by epoxy resin, phenol resin, polyimide, polystyrene, etc. These resins are lower in Young's modulus than the rare earth metal phase. So, the replacement of the RE phase with polymer resin leads to further increased magnetostrictive strain because the elongation of REFe₂phase is constrained less by polymers than by RE.
FIG. 3 a shows a structure of a cross-section of a unidirectionally solidified material, comprising 60 vol % of primary REFe₂phase and 40 vol % of eutectic phase. FIG. 3 b shows a structure of a cross-section of the polymer composite obtained by annealing the material shown in FIG. 3 a at 1000° C. for 6 hours to remove the eutectic phase, and infiltrating the epoxy resin heated to 80° C. into the eutectic phase-removed voids, followed by curing the infiltrated resin.
Finally, the curing process of the infiltrated resin may be carried out via general methods. For example, in case of YD-114 epoxy resin, the resin is maintained at 80° C. for 2 hours and cured. As such, a predetermined pressure may be applied to the composite material in order to collapse pores present in the composite and to prevent formation of bubbles in the resin. The curing of resin is an exothermic reaction and thus thermal stress resides in the cured polymer composite due to different thermal expansion coefficients between the Laves phase and the polymer resin. The Laves phase having a lower thermal expansion coefficient is subjected to compressive residual stress. The magnetostrictive strain of the polymer composite is increased proportionally to the compressive stress parallel to the measuring direction. Thus, the residual thermal stress generated by the above procedure consequently functions to improve the magnetostrictive strain of the composite.
A better understanding of the present invention may be obtained in light of the following examples which are set forth to illustrate, but are not to be construed to limit the present invention.

EXAMPLE 1

Preparation of Polymer Composite using Tb_0.3Dy_0.7Fe_1.32
In the present example, as a giant magnetostrictive material, an alloy comprising 90 vol % of primary REFe₂phase and 10 vol % of eutectic phase was used. In FIG. 4 showing a pseudobinary phase diagram of the alloy, terbium (Tb) and dysprosium (Dy) form a complete solid solution. The “RE” in the drawing means a rare earth phase of Tb_xDy_1-x, and REFe₂is defined as a Laves phase having giant magnetostrictive property.
To prevent the alloy rod from being oxidized at a high temperature, the alloy rod was charged into a quartz tube, which was then filled with highly pure argon gas, and the tube was sealed, followed by performing annealing process at 1000° C. for 6 hours to remove the eutectic phase. A sample having fine open pores was infiltrated with YD-114 epoxy resin as follows. Into a chamber (autoclave) capable of being subjected to evacuation and pressurization, the epoxy resin heated up to 80° C. and the sample were separately charged, and the chamber was evacuated to remove air present in the pores of the sample, followed by dipping the sample into liquid phase epoxy resin and curing it for 2 hours (as such, the pressure of about 5 atm was applied to more easily perform infiltration).
FIG. 5 compares the saturation magnetostrictive strains of the magnetostrictive material having the above composition and the composite produced by the example of the present invention. In the graph, a dotted line shows the saturation magnetostrictive strain of the magnetostrictive material solidified unidirectionally, and a full line shows the saturation magnetostrictive strain of the polymer composite having two times higher magnetostrictive strain than the material represented by the dotted line. In FIG. 5, a transverse axis shows the compressive pre-stress during the measurement of the magnetostrictive strain, in which the magnetostrictive strain of the rare earth-based magnetostrictive material as in the alloy having the above composition varies with the pre-stress.
FIG. 6 compares magnetostrictive curves measured in the state where a compressive stress of 7 Mpa is applied to the material. From this figure, it can be seen that the magnetostrictive strain varies with the strength of the applied magnetic field. In the drawing, the dotted line corresponds to unidirectionally solidified alloy and the full line to the composite material.
Meanwhile, the electric resistances of the unidirectionally solidified alloy and the polymer composite are given in Table 1, below, in which the larger the amount of the epoxy resin substituted for the eutectic phase, the higher the resistivity.

TABLE 1

Measured Electric Resistance

REFe₂Phase Number of Average Resistivity

No. State (vol %) measurements (μΩm)

1 Metal 95 5 8.0

2 Composite 90 10 900

3 Composite 60 10 2500

4 Composite 40 12 20000

INDUSTRIAL APPLICABILITY

According to the present invention, the electric resistance of the magnetostrictive material is increased due to the polymer resin serving as an insulator, and thus eddy current loss can be decreased and toughness of the material can be improved, attributable to the polymer resin network formed in the material structure. Further, by using the polymer resin having lower Young's modulus than the rare earth metals, the magnetostrictive strain of the inventive polymer composite is higher than that of the magnetostrictive material containing the eutectic phase of the same volume fraction as the polymer resin. Furthermore, the preparation method involving the annealing process can increase magnetic properties.
The present invention has been described in an illustrative manner, and it is to be understood that the terminology used is intended to be in the nature of description rather than of limitation. Many modifications and variations of the present invention are possible in light of the above teachings. Therefore, it is to be understood that within the scope of the appended claims, the invention may be practiced otherwise than as specifically described.

Claims

1. A method of preparing a polymer composite the method comprising:

a) removing a eutectic phase from a unidirectionally solidified giant magnetostrictive material to create a rare earth metal phase with voids; and

(b) infiltrating a polymer resin into the voids; and

(c) curing the polymer resin.

2. The method as set forth in claim 1, wherein the removing in (a) is performed by thermally annealing the magnetostrictive material at a higher temperature than a eutectic temperature.

3. The method as set forth in claim 1, further comprising: before the infiltrating step, removing all gases present in the magnetostrictive material under any of an inert gas and a vacuum.

4. The method as set forth in claim 1, further comprising applying pressure to the polymer resin to prevent formation of pores in the polymer resin upon curing.

5. The method as set forth in claim 1, wherein the giant magnetostrictive material comprises a rare earth-iron magnetostrictive alloy.

6. The method as set forth in claim 5, wherein the rare earth-iron magnetostrictive alloy is selected from the group consisting of:

Tb_xDy_1-xFe_2-w(0.27≦x≦0.35, 0≦w≦0.20);
Tb_xHo_1-xFe_2-w(0.10≦x≦1.00, 0≦w≦0.20);
Sm_xDy_1-xFe_2-w(0.80≦x≦1.00, 0≦w≦0.20);
Sm_xHo_1-xFe_2-w(0.60≦x≦1.00, 0≦w≦0.20);
Tb_xHo_yFe_2-w(0.10≦x≦1.00, 0≦y≦0.9, 0≦z≦0.8, 0≦w≦0.20, x+y+z=1); and
Sm_xHo_yDy_zFe_2-w(0.60≦x<1.00, 0≦y≦0.4, 0≦z≦0.4, 0≦w≦0.20, x+y+z=1).

7. A polymer composite prepared by the method of claim 1.

8. The method of claim 1, wherein the removing step is performed by thermally annealing the magnetostrictive material at about 1000° C. for approximately 6 hours.

9. The method of claim 1, wherein the curing step is performed by heating the polymer resin at about 80° C. for approximately 2 hours.

10. The method of claim 1, wherein the polymer resin is selected from the group consisting of epoxy resin, phenol resin, polyimide and polystyrene.

11. The method of claim 1, wherein the polymer composite includes a rare earth metal phase, and wherein the polymer resin has a lower Young's modulus than the rare earth metal phase.

12. The method of claim 1, wherein the unidirectionally solidified giant magnetostrictive material includes about 90% by volume of Laves phase and about 10% by volume of eutectic phase.

13. The method of claim 1, wherein the infiltrated resin is a YD-114 epoxy resin.

14. A method of preparing a polymer composite, the method comprising:

(a) replacing a eutectic phase with a polymer resin, in a giant magnetostrictive material that comprises a rare earth metal phase and the eutectic phase; and

(b) curing the polymer resin.

15. The method of claim 14, further including thermally annealing the magnetostrictive material at a higher temperature than a eutectic temperature to remove the eutectic phase from the magnetostrictive material.

16. The method of claim 14, further comprising, before the replacing, removing all gases present in the magnetostrictive material under any of an inert gas and a vacuum.

17. The method of claim 14, further comprising applying pressure to the polymer resin to prevent formation of pores in the polymer resin upon curing.

18. The method of claim 14, wherein the giant magnetostrictive material comprises a rare earth-iron magnetostrictive alloy.

19. The method of claim 18, wherein the rare earth-iron magnetostrictive alloy is selected from the group consisting of:

Tb_xDy_1-xFe_2-w(0.27≦x≦0.35, 0≦w≦0.20),
Tb_xHo_1-xFe_2-w(0.10≦x≦1.00, 0≦w≦0.20),
Sm_xDy_1-wFe_2-w(0.80≦x≦1.00, 0≦w≦0.20),
Sm_xHo_1-xFe_2-w(0.60≦x≦1.00, 0≦w≦0.20),
Tb_xHo_yDy_zFe_2-w(0.10≦x≦1.00, 0≦y≦0.9, 0≦z≦0.8, 0≦w≦0.20, x+y+z=1), and
Sm_xHo_yDy_zFe_2-w(0.60≦x<1.00, 0≦y≦0.4, 0≦z≦0.4, 0≦w≦0.20, x+y+z=1).

20. The method of claim 14, wherein the polymer resin is a YD-114 epoxy resin.

21. The method of claim 14, wherein the removing step is performed by thermally annealing the magnetostrictive material at about 1000° C. for approximately 6 hours.

22. The method of claim 14, wherein the curing step is performed by heating the polymer resin at about 80° C. for approximately 2 hours.

23. The method of claim 14, wherein the polymer resin is selected from the group consisting of epoxy resin, phenol resin, polyimide and polystyrene.

24. The method of claim 14, wherein the polymer resin has a lower Young's modulus than the rare earth metal phase.

25. The method of claim 14, wherein the giant magnetostrictive material includes about 90% by volume of Laves phase and about 10% by volume of eutectic phase.

26. A polymer composite prepared by the method of claim 14.

27. A polymer composite material comprising:

a Laves phase of a rare earth metal in unidirectionally solidified dendrite form and having a giant magnetostrictive material; and

a polymer resin filling void between the dendrites of the Laves phase.

28. The polymer composite of claim 27, wherein the Laves phase is selected from the group consisting of:

Tb_xDy_1-xFe_2-w(0.27≦x≦0.35, 0≦w≦0.20),
Tb_xHo_1-xFe_2-w(0.10≦x≦1.00, 0≦w≦0.20),
Sm_xDy_1-xFe_2-w(0.80≦x≦1.00, 0≦w≦0.20),
Sm_xHo_1-xFe_2-w(0.60≦x≦1.00, 0≦w≦0.20),
Tb_xHo_yDy_zFe_2-w(0.10≦x≦1.00, 0≦y≦0.9, 0≦z≦0.8, 0≦w≦0.20, x+y+z=1), and
Sm_xHo_yDy_zFe_2-w(0.60≦x≦1.00, 0≦y≦0.4, 0≦z<0.4, 0≦w≦0.20, x+y+z=1).

29. The polymer composite of claim 27, wherein the polymer resin is selected from the group consisting of epoxy resin, phenol resin, polyimide and polystyrene.

30. The polymer composite of claim 27, wherein the polymer resin has a lower Young's modulus than the rare earth metal phase.

31. The polymer composite of claim 27, wherein the giant magnetostrictive material includes about 90% by volume of the Laves phase and about 10% by volume of the polymer resin.

32. The polymer composite of claim 27, wherein the Laves phase comprises a rare earth-iron magnetostrictive alloy.