Patent Application
20220359812
The present invention relates to a piezoelectric material, a piezoelectric member, a piezoelectric element and a pressure sensor.
Sensors or actuators in which a piezoelectric element is used are being used for various applications. In addition, piezoelectric materials, which can be used even in high-temperature environments of several hundred degrees Celsius or higher, are being expected to be applied to, for example, combustion pressure sensors in engines, ultrasonic sensors that constantly monitor high-temperature plants in thermal power stations, and the like.
Preferable characteristics required for piezoelectric materials usable in high-temperature environments are (1) a high phase transition temperature, (2) high electric resistivity even at high temperatures, (3) high temperature stability elicited by piezoelectric characteristics, (4) small pyroelectric characteristics and (5) a high compressive strength, but no materials satisfying these five requirements have been thus far discovered.
As a piezoelectric body of a melilite-type crystal, gehlenite (Ca2Al2SiO7) has been proposed (refer to Patent Document 1). This crystal satisfies requirements of high-temperature resistance, pyroelectric inactivity and high insulating properties, which are required for combustion pressure sensor materials, but has a problem with the compressive strength, i.e., the compressive strength is low in a cutting orientation satisfying the piezoelectric constant d14 of 7.0 pC/N and the piezoelectric constant d36 is as low as 1.0 pC/N in a cutting orientation exhibiting a high compressive strength. In addition, as another piezoelectric body of a melilite-type crystal, akermanite (Ca2MgSi2O7) has also been proposed (refer to Patent Document 2), but akermanite has a problem with phase transition that occurs at near 80° C.
An aspect of the present invention is to provide a piezoelectric material, a piezoelectric member, a piezoelectric element and a pressure sensor that can be used in high-temperature environments.
In order to improve the compressive strength, which is a problem of gehlenite (Ca2Al2SiO7), the present inventors paid attention to akermanite (Ca2MgSi2O7), which belongs to the same melilite-type crystal family (A2BT2O7) as gehlenite, and found a novel piezoelectric single crystal that has overcome the problem of akermanite (phase transition at near 80° C.).
A piezoelectric material according to the present invention is a piezoelectric material composed of Sr-substituted akermanite represented by Ca(2-x)SrxMgSi2O7 (0.1≤x≤0.6). According to the above-described configuration, it is possible to prevent the phase transition of akermanite, and the piezoelectric material satisfies the above-described five requirements.
A piezoelectric member according to the present invention is a piezoelectric member containing, as a main component, the above-described piezoelectric material.
According to the above-described configuration, the piezoelectric member contains, as a main component, the above-described piezoelectric material and is thus dominated by the piezoelectric characteristics of the piezoelectric material. Therefore, this piezoelectric member becomes excellent in terms of temperature stability from room temperature through high-temperature environments.
The piezoelectric member may contain a material other than the above-described piezoelectric material as an accessory component and may contain an impurity that is inevitably contained during production.
The piezoelectric member is preferably cut in an orientation of (ZXt) θ (30°≤θ≤60°) when two a axes of a unit lattice of the tetragonal crystal of the Sr-substituted akermanite are X axis and Y axis and c axis is Z axis. According to the above-described configuration, the piezoelectric member is capable of using a high piezoelectric effect.
A piezoelectric element according to the present invention has the above-described piezoelectric member and at least a pair of electrodes provided on surfaces that are orthogonal to a stress application surface of the piezoelectric member and face each other. According to the above-described configuration, the piezoelectric element is capable of efficiently detecting charges generated due to a transverse piezoelectric effect.
A pressure sensor according to the present invention has a diaphragm and the above-described piezoelectric element. According to the above-described configuration, the pressure sensor detects charges that are generated in the piezoelectric member due to stress that arises from pressure that is applied through the diaphragm and is transmitted to the stress application surface of the piezoelectric member and thereby measures the pressure.
According to the piezoelectric material of the present invention, it is possible to provide a material that satisfies the five requirements of (1) a high phase transition temperature, (2) high electric resistivity even at high temperatures, (3) high temperature stability of piezoelectric characteristics, (4) small pyroelectric characteristics and (5) a high compressive strength. This makes it possible for a piezoelectric member, a piezoelectric element and a pressure sensor in which this piezoelectric material is used to be used even in high-temperature environments.
Hereinafter, embodiments of the present invention will be described with appropriate reference to figures.
[Piezoelectric Material]
A piezoelectric material according to the present embodiment is a piezoelectric material represented by Ca(2-x)SrxMgSi2O7 (0.1≤x≤0.6). That is, the piezoelectric material according to the present embodiment is composed of Sr-substituted akermanite obtained by substituting some of Ca atoms in akermanite (Ca2MgSi2O7) with Sr atoms.
Akermanite (Ca2MgSi2O7) has a high piezoelectric constant of d36=4.3, but phase transition occurs in akermanite at near 80° C. due to the formation of an incommensurate structure. The piezoelectric constant does not disappear even in high-temperature phases, but the piezoelectric constant significantly changes at near this phase transition temperature, which creates a problem with use in sensor application. The present inventors substituted Ca atoms in A sites with Sr atoms to lower the phase transition temperature and suppress the occurrence of phase transition in the vicinity of the operating temperature region, thereby finding a material for combustion pressure sensors that satisfies the above-described five requirements (1) to (5).
Specifically, the piezoelectric material according to the present embodiment exhibits the following effects.
1. Approximately the same piezoelectric constant as quartz is exhibited.
2. Phase transition and pyroelectricity are not shown.
3. The compressive strength is as high as approximately 1 GPa.
4. The change in the piezoelectric constant over temperature is as small as that of langatate.
5. A crystal can be grown by the Czochralski method.
6. Rare elements (lanthanoids and transition elements) are not used.
As described above, the piezoelectric material according to the present embodiment has a high piezoelectric constant, undergoes no phase transition even at high temperatures, does not change significantly in the piezoelectric constant (piezoelectric characteristics) and is stable. That is, the use of the piezoelectric material according to the present embodiment makes it possible to provide piezoelectric elements that can be used even in high-temperature environments.
[Configuration of Piezoelectric Element]
Next, the configuration of a piezoelectric element according to a first embodiment of the present invention will be described with reference to
The piezoelectric element 1 has a pair of the electrode 3 and the electrode 4 provided on two surfaces, which face each other, of the rectangular piezoelectric member 2 excised (cut out) in a predetermined crystal orientation. In addition, when the piezoelectric member 2 deforms due to application of stress, charges are generated on the surfaces of the piezoelectric member 2 in proportion to the stress, that is, in proportion to the amount of deformation, due to the piezoelectric effect (piezo effect). In addition, a voltage E is generated between the electrode 3 and the electrode 4 due to these charges. In addition, when the voltage E is applied between the electrode 3 and the electrode 4, the piezoelectric member 2 deforms in proportion to the applied voltage due to the converse piezoelectric effect (converse piezo effect).
The use of the piezoelectric effect makes it possible to apply the piezoelectric element 1 to a variety of sensors such as pressure sensors or ultrasonic sensors. In addition, the use of the converse piezoelectric effect also makes it possible to apply the piezoelectric element 1 to oscillators, actuators, or the like.
In addition, in the case of being used as a sensor, the piezoelectric element 1 detects charges generated on the surfaces of the piezoelectric member 2 through the electrode 3 and the electrode 4. Here, “detecting charges” means that a physical amount attributed to charges generated by the application of stress to the piezoelectric member 2 is detected (measured). For example, “detecting charges” means that the electric quantity of the generated charges is detected (measured) or a voltage generated between the electrode 3 and the electrode 4 is detected (measured) based on the generated charges.
In addition, in the case of using the piezoelectric material according to the present embodiment as the piezoelectric member 2, the piezoelectric element 1 in which the transverse piezoelectric effect (d31 mode) is used is configured. The transverse piezoelectric effect refers to a piezoelectric effect with which a direction in which stress is applied and the polarization direction of charges that are generated by the application of the stress become orthogonal to each other. In the present embodiment, an end surface of the rectangular piezoelectric member 2 in the longitudinal direction (the front surface or the rear surface in
The transverse piezoelectric effect also generates charges in a polarized manner on the surfaces of the piezoelectric member 2 in a different direction that is orthogonal to the stress application direction (horizontal direction in
(Piezoelectric Member)
The piezoelectric member 2 is a rectangular (plate-shaped) crystal piece cut in a predetermined crystal orientation from a crystal bulk body of the piezoelectric material according to the present embodiment. Specifically, the piezoelectric member 2 is a member cut in an orientation of (ZXt) θ (30°≤θ≤60°) when the two a axes of the unit lattice of the tetragonal crystal of Sr-substituted akermanite are regarded as the X axis and the Y axis and the c axis is regarded as the Z axis.
The two a axes of the unit lattice of the tetragonal crystal are regarded as the X axis and the Y axis and the c axis is regarded as the Z axis. At this time, cutting the crysta in an orientation of (ZXt) θ at an angle θ means that the crystal is cut out on a surface for which the Z axis is a normal line (Z surface), a surface for which an axis obtained by rotating the X axis around the Z axis by θ (XZ axis) is a normal line (XZ surface) and a surface for which an axis obtained by rotating the Y axis around the Z axis by θ (YZ axis) is a normal line (YZ surface). The piezoelectric member 2 shown in
Usually, in a piezoelectric member formed by cutting a tetragonal crystal having piezoelectricity and cleavability in an orientation of (ZXt) θ, when stress is applied to the XZ surface (a surface for which an axis obtained by rotating the X axis around the Z axis by 45° is a normal line), charges are generated on the Z surface (the surface for which the Z axis is a normal line) in a quantity in proportion to the magnitude of the stress. At this time, charges that are generated on the Z surface due to the stress applied to the XZ surface are proportional to the piezoelectric constant d36 and {sin (2θ)}/2. Therefore, in the piezoelectric member 2, θ, which is the rotation angle, is set to 45° in order to maximize the quantity of charges generated. However, θ is not limited to 45°, and, even at rotation angles of 30° to 60°, the charges that are generated on the Z surface due to the stress applied to the XZ surface are capable of securing 85% or more of the charge quantity compared with a case where θ is set to 45°. Therefore, among piezoelectric members obtained by cutting a tetragonal crystal having piezoelectricity and cleavability in an orientation of (ZXt) θ, piezoelectric members for which θ is set in a range of 30° to 60° can be preferably used as a piezoelectric element for pressure sensors. The piezoelectric constant d36 is an intrinsic value of the tetragonal crystal that is used for the piezoelectric member 2.
In a tetragonal crystal having cleavability, an arbitrary surface parallel to a surface for which the Z axis (c axis) of the unit lattice of the tetragonal crystal is a normal line serves as a cleavage surface. Therefore, in the piezoelectric member 2, an arbitrary cross section parallel to a surface for which the Z axis is a normal line serves as a cleavage surface.
As described above, when stress is applied in a direction of the stress application axis, the transverse piezoelectric effect also generates polarized charges on the YZ surface (the surface for which the axis obtained by rotating the Y axis around the Z axis by 45° is a normal line), which is in a different direction that is orthogonal to the stress application axis. Therefore, a piezoelectric element can also be configured by providing electrodes on surfaces for which this axis is a normal line.
In addition, a crystal piece cut out by cutting in a different crystal orientation may also be used as the piezoelectric member 2. In addition, the shape of the piezoelectric member 2 is not limited to the rectangular shape and may have any of a variety of shapes such as a disc shape and a rod shape depending on application.
(Electrodes)
The electrodes 3 and 4 are provided on the charge generation surfaces of the rectangular piezoelectric member 2, respectively. Preferably, the electrodes 3 and 4 are provided on the two Z surfaces, which are the charge generation surfaces of the piezoelectric member 2, respectively. As the electrodes 3 and 4, it is possible to use a metallic material having a higher melting point than high-temperature environments in which the piezoelectric element 1 is used. Particularly, examples of a material that can be used even in high-temperature environments of 800° C. or higher include Au, platinum (Pd), palladium (Pt) and Ag—Pd alloys. In addition, in a case where the electrodes 3 and 4 are used at a relatively low temperature, a Ag paste can also be used.
The electrodes 3 and 4 can be formed on the front surface and the rear surface of the piezoelectric member 2, respectively, using the above-described material by a method such as a coating method, a deposition method, a plating method or a sputtering method.
[Method for Producing Piezoelectric Element]
Next, a method for producing the piezoelectric element 1 will be described with reference to
As shown in
(Crystal Growth Step)
First, in the crystal growth step S10, a crystal bulk body that is a piezoelectric material is produced. The crystal bulk body can be produced as a rod-shaped single crystal by the Czochralski method. The Czochralski method is used as a method for producing semiconductor materials, and the crystal bulk body that is used in the present invention can also be produced using the same crystal growth device.
Here, an example of the crystal growth device by the Czochralski method will be described with reference to
The crucible 11 is a container into which a raw material is injected and which stores melt 23 of the raw material that has been heated and melted with the heating portion 21. As the crucible 11, for example, a container made from iridium (Ir, melting point of approximately 2460° C.), which is a metal having a high melting point, is used.
The crucible 12 is configured to surround the crucible 11 and a crystal pull region and partially forms a double structure such that a favorable heat-retaining property can be obtained. In the present embodiment, as the crucible 12, a zirconia (ZrO2) crucible is used.
In addition, the alumina bubbles 13 are loaded into a gap between the crucible 11 and the crucible 12.
The alumina bubbles 13 are hollow spherical alumina (Al2O3) particles. When the alumina bubbles 13 are loaded into the gap between the crucible 11 and the crucible 12, deformation of the Ir crucible 11 is prevented, and the temperature-retaining property near the crucible 11 can be enhanced.
The quartz tube 14 is a container for holding a reaction atmosphere by covering the outsides of the crucibles 11 and 12, which are reaction portions, and blocking external air. The upper and lower portions of the quartz tube 14 are sealed with the upper lid 15 and the lower lid 16.
The upper lid 15 and the lower lid 16 are provided at the upper end and the lower end of the quartz tube 14, respectively, and are intended to hold the reaction atmosphere together with the quartz tube 14.
The upper lid 15 has a bearing that holds the crystal pull rod 17 in the center so as to be capable of rotating around the central axis of the crystal pull rod 17 and capable of moving in the axial direction. In addition, the gas introducing portion 19 for controlling the reaction atmosphere is provided in a part of the upper lid 15 and configured so as to supply argon (Ar) gas, nitrogen gas or the like.
In addition, the exhaust port 20 is provided in the lower lid 16.
The crystal pull rod 17 is intended to grip a seed crystal 22 at the front end (the lower end in the figure) and to pull a crystal from the melt 23 of the raw material that is held in the crucible 11. The crystal pull rod 17 is gripped by the load cell 18 in the upper portion and configured so as to be capable of rotating around the central axis and moving in the vertical direction by driving means such as a motor, which is not shown.
The load cell 18 is a load meter that grips the upper portion of the crystal pull rod 17 and measures the weights of the crystal pull rod 17 and a crystal that grows at the lower end of the crystal pull rod 17. The load cell 18 controls the crystal growth device 10 so as to stop crystal growth when the weight of the grown crystal reaches a predetermined weight.
The gas introducing portion 19 is provided in the upper lid 15 and is gas introduction control means such as a valve for introducing gas for controlling the reaction atmosphere into the inside of the quartz tube 14.
As the gas that is introduced as the reaction atmosphere, inactive or poorly active Ar gas or nitrogen gas can be used. In addition, a small amount of oxygen gas may be mixed with the above-described gas and introduced into the inside of the quartz tube 14 in order to suppress generation of an oxygen defect in a crystal to be produced.
In addition, the exhaust port 20, which serves as an exit for the flow of the gas that is introduced from the gas introducing portion 19, is provided in the lower lid 16.
The heating portion 21 is heating means for melting the raw material that has been injected into the crucible 11. In the present embodiment, a radiofrequency (RF) coil is provided as the heating portion 21 so as to surround the outside of a region in the quartz tube 14 in which the crucible 11 is disposed. When electric power is supplied to the RF coil, a magnetic field is generated in the RF coil, this magnetic field generates an induced current in the crucible 11, which is metal, and the crucible 11 is heated to a high temperature. Therefore, the raw material that is held in the crucible 11 is melted.
The heating portion 21 is not limited to means for radiofrequency induction heating, and different heating means such as a heater may also be used.
The seed crystal 22 serves as a nucleus for crystal growth at the time of pulling a crystal from the melt 23. The seed crystal 22 is preferably a single crystal of a crystal to be grown, but a polycrystal having the same formulation as the crystal to be grown can also be used. In addition, a platinum (Pt) rod, an Ir rod or the like can also be used.
The seed crystal 22 may have a prism shape, but the shape is not limited thereto. The size of the seed crystal 22 can be appropriately determined depending on the size of the crucible 11 that holds the melt 23 or the size of the crystal to be grown. For example, in a case where the crucible 11 has a cylindrical shape with a size of 50 mm in inner diameter and 50 mm in height, the cross section of the seed crystal 22 may have a prism shape that is 3 mm×3 mm to 5 mm×5 mm and 20 to 50 mm in length.
Next, the crystal growth step S10 of producing a crystal bulk body of a piezoelectric material will be described. The crystal growth step S10 can be carried out using the crystal growth device 10 shown in
First, as raw materials, a compound containing Ca such as powder-form calcium carbonate (CaCO3), a compound containing Sr such as strontium carbonate (SrCO3), a compound containing Mg such as magnesium oxide (MgO) and a compound containing Si such as silicon oxide (SiO2) are weighed and mixed such that a formulation of Ca(2-x)SrxMgSi2O7 (0.1≤x≤0.6) is formed, that is, the mole ratio becomes 2-x:x:1:2.
Next, the powder mixture of the above-described raw materials is put into the crucible 11 and installed in the crystal growth device 10. In addition, Ar gas or nitrogen gas is introduced from the gas introducing portion 19 to adjust the reaction atmosphere. At this time, a small amount of oxygen gas may be mixed and introduced from the gas introducing portion 19.
In addition, the seed crystal 22 is mounted in the front end of the crystal pull rod 17.
The seed crystal 22 is preferably a single crystal of the piezoelectric material according to the present embodiment as described above, but may be a polycrystal with the same formulation, or a Pt rod, an Ir rod or the like may be used.
Next, electric power is supplied to the RF coil as the heating portion 21 from a power supply, which is not shown, and the raw materials in the crucible 11 are melted by the radiofrequency induction heating of the crucible 11.
Next, the crystal pull rod 17 is lowered to immerse the seed crystal 22 into the melt 23 of the raw materials. In addition, the crystal pull rod 17 is slowly pulled upward at a predetermined rate while being slowly rotated in a predetermined direction at a predetermined rotation rate. The rotation rate and pulling rate of the crystal pull rod 17 are appropriately set depending on the size of the crystal to be grown.
A rod-shaped single crystal bulk body of the piezoelectric material according to the present embodiment is produced with the above-described operations.
(Crystal Cutting-Out Step)
Next, in the crystal cutting-out step S11, a crystal piece is cut out as the piezoelectric member 2 from the crystal bulk body produced in the crystal growth step S10 by cutting in a predetermined crystal orientation, for example, cutting in (ZXt) 45° indicated by II in
In addition, the surface of the cut-out piezoelectric member 2 may be mirror-polished as necessary.
(Electrode Forming Step)
Next, in the electrode forming step S12, the electrode 3 and the electrode 4 are formed on the front surface and rear surface of the piezoelectric member 2 cut out in the crystal cutting-out step S11, respectively.
The electrodes 3 and 4 can be formed on the piezoelectric member 2 by applying a paste of a powder-form metallic material to the surfaces thereof on which the electrodes 3 and 4 are to be formed. A baking treatment may be further carried out after the application. In addition, the electrodes 3 and 4 may be formed by a deposition method, a plating method, a sputtering method or the like depending on the application.
The piezoelectric element 1 is produced by the above-described steps.
[Configuration of Pressure Sensor]
Next, an example of a pressure sensor in which the piezoelectric element according to the present embodiment is used will be described with reference to
A pressure sensor 30 is made up of a case material 31, a diaphragm 32, an insulating sleeve 33, a base 34, the piezoelectric element 1, an alumina plate 35, a sealing material 36, a fixing screw 37 and electric wires 38 and 39 as shown in
The pressure sensor 30 according to the present embodiment is directly attached to, for example, a combustion chamber in order to measure the combustion chamber pressure of an engine. That is, the pressure sensor 30 is a sensor that can be used in high-temperature environments. Therefore, each member that configures the pressure sensor 30 is formed using a heat-resistant material capable of withstanding several hundred degrees Celsius or higher.
The pressure sensor 30 transmits stress generated due to pressure applied to the diaphragm 32 to the piezoelectric member 2 in the piezoelectric element 1 through the base 34 and detects charges that are generated in proportion to the magnitude of the stress transmitted to the piezoelectric member 2 on the charge generation surfaces provided with the electrodes 3 and 4 of the piezoelectric element 1 with charge detection means (not shown) such as an electric quantity measuring instrument or a voltage measuring instrument that is connected to the electric wires 38 and 39, thereby measuring the pressure.
In the present embodiment, the piezoelectric element 1 converts stress (pressure) applied to the piezoelectric member 7 to a charge quantity using the transverse piezoelectric effect. The pressure sensor 30 according to the present embodiment measures pressure applied to the diaphragm 32 based on the charge quantity detected through the electrodes 3 and 4 in this piezoelectric element 1.
The case material 31 is a cylindrical stainless steel case. The diaphragm 32 is provided at the lower end of the case material 31. The diaphragm 32 is a disc-shaped stainless steel member, and the lower surface of the diaphragm 32 is a pressure-receiving surface that receives pressure, which is the measurement subject. The piezoelectric element 1 is provided on the upper surface of the diaphragm 32 through the glass base 34.
In addition, the alumina insulating sleeve 33 is provided between the piezoelectric element 1 and the inner circumferential surface of the case material 31 and between the base 34 and the inner circumferential surface of the case material 31.
As the piezoelectric element 1 in the present embodiment, the piezoelectric element 1 according to the first embodiment shown in
In addition, in order to use the transverse piezoelectric effect in the piezoelectric element 1, the electrodes 3 and 4 are provided to face each other in a transverse direction, which is a direction that is orthogonal to a direction in which stress that the piezoelectric member 2 receives is applied, or in the transverse direction and a direction perpendicular to the paper on the side surfaces of the piezoelectric member 2.
The shape of the piezoelectric element 1 may be a prism shape as shown in
In addition, the electrode 3 and the electrode 4 in the piezoelectric element 1 are electrically connected to ends on one side of the electric wire 38 and the electric wire 39, respectively. The electric wires 38 and 39 are preferably electric wires coated with ceramic felt that is heat-resistant enough to be used in high-temperature environments. In addition, as shown in
The alumina plate 35, which is an insulating member, is provided on the upper surface side of the piezoelectric element 1, and furthermore, the stainless steel sealing material 36 is provided on the upper portion of the alumina plate 35. In addition, the case material 31 is joined to the diaphragm 32 and the sealing material 36 at places indicated by “white letter X's” in (a) of
In addition, the fixing screw 37 is provided in the central portion of the sealing material 36 in a plan view and passes through the sealing material 36. The front end of the fixing screw 37 is screwed up to approximately the center of the alumina plate 35 in the thickness direction. The fixing screw 37 fixes the positions of the individual members that are disposed in the case material 31. As the fixing screw 37, for example, a Fe—Ni-based alloy fixing screw can be used.
The shape of the case material 31 is not limited to the cylindrical shape and can also be made into a quadratic prism shape, a polygonal prism shape or the like. In addition, the pressure sensor 30 can also be configured to, for example, be provided with a screw thread on the outer circumference of the front end portion of the case material 31 and be screwed into a predetermined mounting hole that communicates with an engine combustion chamber by the same method as for mounting of spark plugs, thereby being mounted.
[Operation of Pressure Sensor]
Next, the operation of the pressure sensor 30 will be subsequently described with reference to
The pressure sensor 30 receives pressure in a combustion chamber or the like in an engine on the pressure-receiving surface, which is the lower surface of the diaphragm 32. Stress generated due to the pressure received by the diaphragm 32 is transmitted to the piezoelectric member 2 in the piezoelectric element 1 through the base 34. The piezoelectric member 2 deforms due to the transmitted stress and generates charges in proportion to the amount of deformation due to the transverse piezoelectric effect. Positive and negative charges generated in the piezoelectric member 2 are measured with the charge detection means (not shown) connected through the electrodes 3 and 4 and the electric wires 38 and 39 as physical amounts such as a voltage or an electric quantity attributed to the generated charges. The pressure received by the diaphragm 32 can be obtained based on the measured voltage, electric quantity or the like.
Determination of Synthesis Formulation by DSC
First, for samples of individual formulations, the occurrence of phase transition was inspected by DSC measurement.
For formulations of Ca(2-x)SrxMgSi2O7 (x=0, 0.05, 0.10, 0.30 and 0.60), powder-form samples were produced. As raw materials, CaCO3, SrCO3, MgO and SiO2, all of which had a purity of 99.99%, were used.
The raw materials were weighed, mixed in a wet manner in an agate mortar and calcinated in a platinum crucible at 1250° C. under conditions of a temperature rise rate of 15° C./min and a holding time of four hours. The calcinated powders were pulverized in a wet manner in the agate mortar and CIP-molded into a rod shape at 100 MPa. The rods were fired on a platinum plate at 1350° C. under conditions of a temperature rise rate of 15° C./min and a holding time of four hours, and sintered bodies were cut out in a finer rod shape with a low-speed diamond cutter and partially melted and recrystallized by heating by light concentration of a CO2 laser. Recrystallized portions were pulverized in a wet manner in the agate mortar, and crystal phases were confirmed by powder XRD. As a result, intended crystal structures were obtained, and no foreign phases were confirmed. Therefore, it was determined that DSC measurement was to be carried out using these powders.
The individual produced samples of Ca(2-x)SrxMgSi2O7 (x=0, 0.05, 0.10, 0.30 and 0.60) were pulverized, then, sufficiently dried at 120° C. in a drying furnace, and then measured. As the reference sample, Al2O3 powder was used, and the individual samples were put into alumina containers, respectively, and measured in a sealed state. The measurement was carried out twice. In the first measurement, the individual samples were measured in a range of room temperature to 400° C. at a temperature rise rate of 20° C./min in order to grasp the tendencies of the samples. In the second measurement, samples that had been selected as candidates based on the results of the first measurement were cooled using liquefied nitrogen in a range of 500° C. to −60° C. at 20° C./min and measured. DSC curves obtained from the second measurement are shown in
From these results, it was found that the peaks of phase transition became blunt with x of 0.10 or more and the peaks of phase transition were not shown with x of 0.30 or more. Based on these results, the formulations for which a single crystal was to be grown were determined as x=0.10 and 0.30.
Single Crystal Growth by Czochralski (Cz) Method
Raw materials were prepared according to formulations of Ca(2-x)SrxMgSi2O7 (x=0.10, 0.30). As the raw materials, similar to those for the DSC samples, CaCO3, SrCO3, MgO and SiO2, all of which had a purity of 99.99%, were used. The raw materials were weighed and calcinated on a platinum plate at 1250° C. at a temperature rise rate of 15° C./min for a holding time of four hours. The calcinated powders were pulverized with a ball mill and molded into a pellet shape with φ44 by uniaxial pressing at 100 MPa. The pellets were fired on the platinum plate at 1350° C. at a temperature rise rate of 15° C./min for a holding time of four hours and loaded into an Ir crucible for single crystal growth. The raw materials in the Ir crucible were melted in an Ar atmosphere using a heating portion of a single crystal growth device. The raw materials were slowly cooled after being confirmed to be completely melted, and a sintered body was added thereto. These operations were repeated, and melt was prepared as much as approximately 80% of the volume of the Ir crucible.
The produced melts were held for one hour in a completely molten state, the absence of air bubbles on the liquid surface was visually confirmed, and then a seed crystal that had been rotated at 15 rpm was brought into contact with the liquid surface. In the case of the single crystal growth with x=0.10, it was not possible to prepare a single crystal of Sr-substituted akermanite that was to serve as a seed crystal, and a polycrystal with the same formulation was thus used. In a case where the seed crystal was melted after the contact, the output of a radiofrequency oscillator was lowered, and, conversely, in a case where a large amount of the melt crystallized, the output was raised, thereby confirming an output with which stable growth could be expected. In the initial phase of the growth, the output was adjusted such that the thickness of a crystal to be grown became approximately 5 mm, and the crystal was grown at a pulling rate of 1.5 mm/h for approximately five hours.
Next, the output of the radiofrequency oscillator was adjusted such that the diameter of the single crystal estimated from the value of the load cell with the pulling rate of the axis set to 1 mm/h became thick at 2 mm/h, and, once the diameter reached approximately 20 mm, the single crystal was grown such that the diameter became constant. In the growth of this straight torso portion, the output was adjusted every 30 minutes such that the diameter became constant.
The straight torso portion was continuously grown until the value of the load cell showed an unnatural change. At the time of ending the growth, the pulling rate was changed to 1.5 mm/h, the output was then adjusted such that a change in the diameter of the crystal to be grown reached −3 mm/h, and the crystal was cut away from the melt.
For Ca(2-x)SrxMgSi2O7 (x=0.10), it was possible to grow a colorless transparent crystal.
A rod that was long in the a-axis direction was cut out from the single crystal with x=0.10 and used as a seed crystal for growing a single crystal with x=0.30. On this formulation as well, single crystal growth was carried out in the same manner.
Determination of Crystal Axis by Back-Reflection Laue Method and Cutting-Out
For Ca(2-x)SrxMgSi2O7 (x=0.10), since a boundary between single crystals was configured in a plane, the single crystals were cut out along the boundary surfaces using a diamond cutter. The cut-out single crystal was fixed to a goniometer, and a Laue photograph of the cut-out surface was captured using a back-reflection Laue X-ray device (Rigaku, Geiger flex). The exposure time to X-rays was set to approximately one minute, and the set values of the tube voltage and the tube current for generation of X-rays were set to 40 kV and 25 mA, respectively. As a target, tungsten was used such that continuous X-rays having a high intensity could be obtained.
For Ca(2-x)SrxMgSi2O7 (x=0.30), since a plane was confirmed in an orientation in which a side surface of a crystal grown in the a axis was divided into four parts, a Laue photograph was captured from one surface thereof.
This confirmed that the grown crystals of Ca(2-x)SrxMgSi2O7 (x=0.10, 0.30) were all single crystals.
After the determination of the orientations of the individual samples, Z-cut plate-shaped samples having a thickness of 1 mm in a direction perpendicular to the c axis were cut out with a wire saw. Furthermore, plate-shaped samples for piezoelectric measurement (1×3×12 mm3) of (ZXt) 45° were cut out from these samples as piezoelectric members. Chips generated during the cutting-out were removed by polishing with #2000 waterproof abrasive paper, sputtering was carried out under conditions of 5 mA and 10 minutes using Au as a target, and electrodes were formed on the front surfaces and rear surfaces of the cut-out piezoelectric members.
Piezoelectric elements were produced in the above-described order.
Next, for samples of the produced piezoelectric elements, the piezoelectric constants d′31 at room temperature were measured as the characteristic values of the piezoelectric elements. In the measurement of the piezoelectric constants d′31, resonant and antiresonant frequencies were measured using an impedance analyzer (Agilent, 4294A), and the piezoelectric constants d′31 were determined based on the measured frequencies. The obtained piezoelectric constants are shown in Table 1.
As a result, it was confirmed that, in Ca(2-x)SrxMgSi2O7 (x=0.10, 0.30), values approximately the same as the piezoelectric constant d12 (=2.3 pCN) of quartz were obtained, and the values were sufficient piezoelectric constants as piezoelectric elements.
Next, the impedances were measured in a state where the samples were put into an electric furnace, and the piezoelectric constants were measured in a range of room temperature to 400° C.
For Ca(2-x)SrxMgSi2O7 (x=0.10) (expressed as CSMS010 in
Next, for the samples of the piezoelectric elements produced as the examples and samples of piezoelectric elements produced using different piezoelectric materials as comparative examples, the piezoelectric constants dij and the electric resistivity were measured as the characteristic values of the piezoelectric elements at different temperatures.
The piezoelectric materials used in the comparative examples are GaPO4 (gallium phosphate), CTGS (Ca3TaGa3Si2O14), CTAS (Ca3TaAl3Si2O14), LTGA (La3Ta0.5Ga5.5-xAlxO14), LTG (La3Ta0.5Ga5.5O14), LGS (La3Ga5SiO14) and YCOB (YCa4O(BO3)3).
An impedance analyzer (HP4294A) manufactured by Hewlett-Packard Company was used for the measurement of the individual characteristic values. The piezoelectric constants di were obtained by measuring and calculating the electromechanical coupling coefficients (kij and kp) of the individual samples by a resonant and antiresonant method. In addition, the electric resistivity was measured by a three-terminal method. The piezoelectric constant that is expressed as di is only the piezoelectric constant d31 of CSMS030, which is because the other crystals were evaluated with d11. The reason for the fact that d11 and d31 may be compared with each other is that those piezoelectric constants serve as a performance index for using the materials as devices.
d*=(dij at each temperature)/(dij at room temperature) Equation (1)
Room temperature refers to a temperature within a range of 15° C. to 35° C.
As shown in
In addition, as shown in
For the samples cut out from the crystal bulk body of Ca(2-x)SrxMgSi2O7 (x=0.30) into a (1×1×2.5 mm3) rod shape in an orientation of (ZXt) 45°, the compressive break strengths were measured using a compression tester. The compression rate was set to 1 mm/min. The number of measurement samples was set to 16, and the compressive break strengths were measured at room temperature.
As described above, the use of Sr-substituted akermanite represented by Ca(2-x)SrxMgSi2O7 (0.1≤x≤0.6) as a piezoelectric material makes it possible to produce piezoelectric elements that can be used in high-temperature environments.
In addition, the produced piezoelectric elements can be used as sensors such as pressure sensors or ultrasonic sensors. For such pressure sensors, application as the above-described combustion pressure sensors in combustion chambers of engines is conceivable. In addition, it is conceivable as application that the ultrasonic sensors are installed in the external walls of boilers, steam piping, turbines or the like in high-temperature plants in thermal power stations to monitor the high-temperature plants.
The application of the piezoelectric element according to the present invention is not limited thereto. Since the Sr-substituted akermanite represented by Ca(2-x)SrxMgSi2O7 (0.1≤x≤0.6) undergoes no phase transition and has no Curie temperature until the melting point, in principle, piezoelectric elements produced using the Sr-substituted akermanite as a piezoelectric material can be used in a broad range of application as elements that can be used in broad temperature environments from room temperature through lower than the melting point of the Sr-substituted akermanite.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2019-121445 | Jun 2019 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2020/024226 | 6/19/2020 | WO |
