Abstract:
A method for manufacturing a cofired multi-layer piezoelectric transformer device includes forming first and second green shapes of a sinterable ceramic composition and applying metallization layer therebetween. Upon cofiring, the composite structure comprises first and second electroactive members bonded together by a conductive layer therebetween. External electrodes are applied and the electroactive members are polarized in a thickness direction, between their two major faces. The first and second electroactive members are arranged such that deformation of one electroactive member results in corresponding deformation of the other electroactive member. The device provides substantial transformation ratios in which relatively high power may be transferred in relation to the size of the unit, operability over wide input and output frequency bandwidths, and electrical isolation of the input voltage and current from the output voltage and current.

Description:
BACKGROUND OF THE INVENTION 
     1. Field of Invention 
     The present invention generally relates to flextensional piezoelectric transformers and actuators, and more particularly, to a method of manufacturing a flextensional multi-layer piezoelectric transformer/actuator by cofiring the ceramic composition with the electrode forming metallization. 
     2. Description of the Prior Art 
     Wound-type electromagnetic transformers have been used for generating high voltage in internal power circuits of devices such as televisions or in charging devices of copier machines which require high voltage. Such electromagnetic transformers take the form of a conductor wound onto a core made of a magnetic substance. Because a large number of turns of the conductor are required to realize a high transformation ratio, electromagnetic transformers that are effective, yet at the same time compact and slim in shape are extremely difficult to produce. 
     To remedy this problem, piezoelectric transformers utilizing the piezoelectric effect have been provided in the prior art. In contrast to the general electromagnetic transformer, the piezoelectric ceramic transformer has a number of advantages. The size of a piezoelectric transformer can be made smaller than electromagnetic transformers of comparable transformation ratio. Piezoelectric transformers can be made nonflammable, and they produce no electromagnetically induced noise. 
     Materials exhibiting piezoelectric and electrostrictive properties develop a polarized electric field when placed under stress or strain. Conversely, they undergo dimensional changes in an applied electric field. The dimensional change (i.e., expansion or contraction) of a piezoelectric or electrostrictive material is a function of the applied electric field. 
     The ceramic bodies employed in prior piezoelectric transformers take various forms and configurations, including rings, flat slabs and the like. A typical example of a prior piezoelectric transformer is illustrated in FIG.  1 . This type of piezoelectric transformer is commonly referred to as a “Rosen-type” piezoelectric transformer. The basic Rosen-type piezoelectric transformer was disclosed in U.S. Pat. No. 2,830,274 to Rosen, and numerous variations of this basic apparatus are well known in the prior art. The typical Rosen-type piezoelectric transformer comprises a flat ceramic slab  10  which is appreciably longer than it is wide and substantially wider than thick. As shown in FIG. 1, a piezoelectric body  10  is employed having some portions polarized differently from others. In the case of FIG. 1, the piezoelectric body  10  is in the form of a flat slab which is considerably wider than it is thick, and having greater length than width. A substantial portion of the slab  10 , the portion  12  to the right of the center of the slab is polarized longitudinally, whereas the remainder of the slab is polarized transversely to the plane of the face of the slab. In this case the remainder of the slab is actually divided into two portions, one portion  14  being polarized transversely in one direction, and the remainder of the left half of the slab, the portion  16  also being polarized transversely but in the direction opposite to the direction of polarization in the portion  14 . 
     In order that electrical voltages may be related to mechanical stress in the slab  10 , electrodes are provided. If desired, there may be a common electrode  18 , shown as grounded. For the primary connection and for relating voltage at opposite faces of the transversely polarized portion  14  of the slab  10 , there is an electrode  20  opposite the common electrode  18 . For relating voltages to stress generated in the longitudinal direction of the slab  10 , there is a secondary or high-voltage electrode  22  cooperating with the common electrode  18 . The electrode  22  is shown as connected to a terminal  24  of an output load  26  grounded at its opposite end. 
     In the arrangement illustrated in FIG. 1, a voltage applied between the electrodes  18  and  20  is stepped up to a high voltage between the electrodes  18  and  22  for supplying the load  26  at a much higher voltage than that applied between the electrodes  18  and  20 . 
     A problem with prior piezoelectric transformers is that they are difficult to manufacture because individual ceramic elements must be “poled” at least twice each, and the direction of the poles must be different from each other. 
     Another problem with prior piezoelectric transformers is that they are difficult to manufacture because it is necessary to apply electrodes not only to the major faces of the ceramic element, but also to at least one of the minor faces of the ceramic element. 
     Another problem with prior piezoelectric transformers is that they are difficult to manufacture because, in order to electrically connect the transformer to an electric circuit, it is necessary to attach (i.e. by soldering or otherwise) electrical conductors (e.g. wires) to electrodes on the major faces of the ceramic element as well as on at least one minor face of the ceramic element. 
     Another problem with prior piezoelectric transformers is that the voltage output of the device is limited by the ability of the ceramic element to undergo deformation without cracking or structurally failing. It is therefore desirable to provide a piezoelectric transformer which is adapted to deform under high voltage conditions without damaging the ceramic element of the device. 
     Piezoelectric and electrostrictive devices (generally called “electroactive” devices herein) are also commonly used as drivers, or “actuators,” due to their propensity to deform under applied electric fields. When used as an actuator, it is frequently desirable that the electroactive device be constructed so as to generate relatively large deformations and/or forces from the electrical input. Prior electroactive devices include flextensional transducers which are composite structures composed of a piezoelectric ceramic element and a metallic shell, stressed plastic, fiberglass, or similar structures. The actuator movement of conventional flextensional devices commonly occurs as a result of expansion in the piezoelectric material which mechanically couples to an amplified contraction of the device in the transverse direction. By coupling two or more electroactive devices, the deformation of one “actuator” can cause the deformation of the adjacent coupled actuator. 
     Another type of transformer, which is disclosed in co-pending patent application Ser. No. 08/864,029 takes advantage of both the electrical properties of electroactive devices as well as the mechanical “actuator” properties. As disclosed in my copending patent application, a piezoelectric transformer can be made by mechanically bonding electroactive devices to each other such that an input voltage is transformed into mechanical movement, which is translated through the mechanical bond to the adjacent electroactive device, which generates an output voltage. 
     One embodiment of the type of piezoelectric transformer disclosed in my co-pending patent application is illustrated in FIG.  2 . This transformer  1  is manufactured by stacking two ceramic wafers  30  and  48  between three preferably metallic layers  36 ,  42  and  54 , bonding them together with four adhesive layers  34 ,  40 ,  44  and  52 , and simultaneously heating the stack to a temperature above the melting point of the adhesive materials, such as LaRC-SI™ developed by NASA Langley Research Center. The adhesive used is a very strong adhesive and has a coefficient of thermal contraction which is greater than that of most ceramics (and, in particular, is greater than that of the materials of the two ceramic wafers  30  and  48 ). The adhesive is used to apply a bond between the respective metallic layers  36 ,  42  and  54  and the ceramic wafers  30  and  46  and the bond is sufficient to transfer longitudinal stresses between adjacent layers of the transformer  1 . 
     After the entire stack of laminate layers have been heated to a temperature above the melting point of the adhesive materials, the entire stack of laminate layers is then permitted to cool to ambient temperature. As the temperature of the laminate layers falls below the melting temperature of the adhesive materials, the four adhesive layers  34 ,  40 ,  44  and  52  solidify, bonding them to the adjacent metallic layers  36 ,  42  and  54 . During the cooling process the ceramic wafers  30  and  42  become compressively stressed along their longitudinal axes due to the relatively higher coefficients of thermal contraction of the materials of construction of the metallic layers  36 ,  42  and  54 . By compressive stressing the two ceramic members  30  and  42 , the ceramic members  30  and  42  are less susceptible to damage (i.e. cracking and breaking). 
     A piezoelectric transformer constructed in accordance with the preceding description comprises a pair of piezoelectric ceramic wafers  30 , and  42  which are intimately bonded to each other (albeit separated by laminated adhesive  34 ,  40 ,  44  and  52  and metallic layers  36 ,  42  and  54 ) along one of each of their major faces. The metallic layers  36 ,  42  and  54  and the four adhesive layers  34 ,  40 ,  44  and  52  are longer than the two ceramic wafers  30  and  42  and, accordingly, protrude beyond the ends of the ceramic members  30  and  42 . Electric terminals  56 ,  58  and  60  are connected (e.g. by wire and solder, or other common means) to an exposed surface of the metallic layers  36 ,  42  and  54  respectively. 
     Referring again to FIG.  2 : When a primary (i.e. input) voltage V 1  is applied across terminals  58  and  60  connected to the electrodes  32  and  38  of the first ceramic wafer  30 , the first ceramic wafer  30  will piezoelectrically generate an extensional stress commensurate with the magnitude of the input voltage V 1 , the piezoelectric properties of the wafer  30  material, the size and geometry of the wafer  30  material, and the elasticity of the other materials of the other laminate layers (i.e. the ceramic wafer  48 , the three pre-stress layers  36 ,  42  and  54 , and the four adhesive layers  34 ,  40 ,  44  and  52 ) which are bonded to the first wafer  30 . The extensional stress which is generated by the input voltage Vi causes the first ceramic wafer  30  to be longitudinally strained, (for example as indicated by arrow  64 ). 
     Because the first ceramic wafer  30  is securely bonded to the second ceramic wafer  48  (i.e. by adhesive layers  40  and  44 ), any longitudinal strain  64  of the first ceramic wafer  30  will result in a longitudinal strain (of the same magnitude and direction) in the second ceramic wafer  48  (as indicated by arrow  65 ). The longitudinal strain  65  of the second piezoelectric ceramic wafer  48  generates a voltage potential V 2  across the two electroplated surfaces  46  and  50  of the second ceramic wafer  48 . The electric terminals  58  and  56  may be electrically connected to corresponding electroplated surfaces  46  and  50  of the second ceramic wafer  48 . The magnitude of the piezoelectrically generated voltage V 2  between the two electrodes  46  and  50  of the second ceramic wafer  48  depends upon the piezoelectric properties of the wafer  48  material, the size, geometry and poling of the wafer  48  material. 
     Thus, by applying a first voltage V 1  across the electroplated  32  and  38  major surfaces of the first ceramic wafer  30 , the first ceramic wafer  30  is caused to longitudinally strain  64 , which, in turn, causes the second ceramic wafer  48  to longitudinally strain  65  a like amount, which, in turn produces a second voltage potential V 2  between the electroplated  46  and  50  major surfaces of the second ceramic wafer  48 . 
     The ratio of the first voltage V 1  to the second voltage V 2  is a function of the piezoelectric properties of the wafer  30 s and  48 , the size and geometry of the wafers  30  and  48  material, the elasticity of the other materials of the other laminate layers (i.e. the ceramic wafers  30  and  48 , the three pre-stress layers  36 ,  42  and  54 , and the four adhesive layers  34 ,  40 ,  44  and  52 ), and the poling characteristics of the two ceramic wafers  30  and  48 . 
     In the one embodiment of the invention disclosed in my co-pending patent application, the facing electroplated surfaces  38  and  46  of the first ceramic wafer  30  and second ceramic wafer  48 , respectively, are electrically connected to a common electric terminal  58 . In alternative embodiments of the transformer (not shown) the corresponding facing electroplated surfaces  38  and  46  of two ceramic wafers  30  and  48  are electrically insulated from each other, (for example by a dielectric adhesive layer), and connected to corresponding terminals. In this modified embodiment of the transformer the two piezoelectric ceramic wafers  30  and  48  are completely electrically isolated from each other. A transformer constructed in accordance with this modification of the invention may be used in an electric circuit to electrically protect electrical components “downstream” from the transformer from damage from high current discontinuities “upstream” of the transformer. 
     Although, this type of piezoelectric transformer is simpler to manufacture than prior art Rosen transformers, it is still somewhat difficult to manufacture because the necessity of adhering electrodes between the ceramic wafers and to the major faces of the ceramic wafers. 
     Another problem with such methods of manufacturing piezoelectric transformers is that it is difficult to maintain complete electrical contact over the entire major face of the ceramic wafer, because of the presence of multiple adhesive layers between the ceramic and metallic layers. 
     Another problem with piezoelectric transformers manufactured by such a process is that the adhesive bond between the metallic layer and ceramic layer may not be uniform, and the adhesive may delaminate or detach due to deformation of the ceramic layer. 
     Another problem is that the presence of multiple adhesive layers between the metallic and ceramic layers makes miniaturization of piezoelectric transformers more difficult using such methods of manufacturing. 
     Another problem with piezoelectric transformers manufactured by such a process is that the multiple adhesive and metallic layers between ceramic layers dampen the motion of the first ceramic layer and limit the translation of motion from the first ceramic layer to the adjacent ceramic layer. 
     SUMMARY OF THE INVENTION 
     The term piezoelectric transformer is here applied to an electrical energy-transfer device employing the piezoelectric properties of co-joined materials to achieve the transformation of voltage or current or impedance. It is an object of the invention to provide a piezoelectric transformer which, in a preferred embodiment is not only capable of substantial transformation ratios, but in which relatively high power may be transferred in relation to the size of the unit. 
     Accordingly, it is a primary object of the present invention to provide a piezoelectric transformer which may be easily and inexpensively produced. 
     It is another object of the present invention to provide a device of the character described which is capable of producing high voltages and which may safely be used in high voltage circuits. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described comprising a pair of ceramic elements, each exhibiting piezoelectric properties, which are in physical (mechanical) communication with each other such that deformation of one ceramic element results in corresponding deformation of the other ceramic element. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which is easy to manufacture because it is sufficient to pole each ceramic element only once, and wherein the direction of poling for each ceramic element is constant over its entire mass. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which is easy to manufacture because it is sufficient have electrodes only on the major faces of the ceramic elements, and which do not require application of electrodes to minor faces of the ceramic elements. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which is easy to manufacture because it is sufficient to apply electrodes only to two parallel faces of the ceramic elements. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which is easy to connect or install in an electric circuit, because it is sufficient to attach (i.e. by soldering or otherwise) electrical conductors (e.g. wires) only to electrodes on the major faces of the ceramic element. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which is adapted to deform under high voltage conditions without damaging the ceramic element of the device. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which is operable over wide input and output frequency bandwidths. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which electrically isolates the voltage and current at the input to the device from the voltage and current at the output of the device. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the translation of motion from one ceramic layer to another ceramic layer is not dampened by an interposed adhesive layer. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the translation of motion from one ceramic layer to another ceramic layer is not substantially dampened by an interposed metallic layer. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described which may be constructed without the use of adhesives. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the metallization adheres well to adjacent ceramic layers. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the metallization has similar mechanical characteristics to the adjacent ceramic layers. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the metallization has thermal expansion characteristics similar to a ceramic. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the metallization has desirable electrical characteristics for use in a piezoelectric transformer. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the metallization is less expensive than conventional metallization (electrode) materials used in piezoelectric transformers. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the formation of piezoelectric ceramic layers occurs simultaneously with the bonding of electrodes (metallization) to the ceramic layer. 
     It is another object of the present invention to provide a piezoelectric transformer of the character described in which the metallization has desirable thermal and oxidation characteristics for use in a cofired piezoelectric transformer. 
     Further objects and advantages of the invention will become apparent from a consideration of the drawings and ensuing description thereof. 
    
    
     BRIEF DESCRIPTION OF THE DRAWINGS 
     FIG. 1 is a perspective view showing the construction of a Rosen-type piezoelectric transformer of the prior art; 
     FIG. 2 is a perspective view showing the construction of a piezoelectric transformer using adhesives for bonding adjacent laminate layers; 
     FIG. 3 is a flow diagram showing the steps of the cofiring process for producing a piezoelectric transformer in accordance with the preferred embodiment of the present invention; 
     FIG. 4 is a perspective view showing a piezoelectric transformer constructed in accordance with the preferred embodiment of the present invention; 
     FIG. 5 is a perspective view of a modified embodiment of the invention; and 
     FIG. 6 is a perspective view of a modified embodiment of the invention. 
    
    
     DESCRIPTION OF THE PREFERRED EMBODIMENTS 
     With reference directed toward the appended drawings, a piezoelectric transformer/actuator (generally designated by the reference numeral  2 ) manufactured embodying the principles and concepts of the present invention will be described. 
     As will be described more fully herein below, a piezoelectric transformer/actuator  2  is manufactured, in part, by first mixing a ceramic powder with a binder (step  100 ); forming green ceramic shapes (step  102 ); applying electrode materials (steps  104  and  114 ); and cofiring the composite structure (steps  106 ,  108 ,  110  and  112 ). 
     Referring to FIG.  3 : FIG. 3 is a flow diagram showing the steps in the preferred embodiment of the present invention, with individual steps denoted by three-digit reference indicia. The first step in the preferred embodiment of the present invention is to mix  100  a ceramic powder with an appropriate amount of a binder. This mixture of a powder and binder forms a sinterable ceramic composition which can produce an electrical ceramic upon firing the mixture. 
     A variety of electrical ceramic materials exist, such as might be or are used in electroactive devices (for example, lead titanate, PbTiO3; lead zirconate titanate, “PZT”; lanthanum doped PZT, “PLZT”; barium titanate, BaTiO3; lithium niobate, LiNbO3; bismuth titanate, Bi4Ti3O12; Aluminum Nitride, AlN; and yttrium barium copper oxide, YBa2Cu3O7. Other electrical ceramics include piezoelectric crystals which are grown, such as lithium gallium oxide, β-LiGa02; lithium aluminum oxide, LiA102; lithium tantalate; LiTaO3; and calcium pyroniobate, Ca2Nb207. Other electrical ceramics include those which are based on the above listed ceramics doped with small amounts of other materials to alter their electrical and/or mechanical properties 
     Production of sinterable ceramic compositions is known in the art. For example, lead zirconate titanate (PZT) is an often used ceramic for piezoelectric applications. Optimum material properties are obtained in the production of PZT when the titanium/zirconium ratio is exactly matched at least in the range of a few thousandths, with respect to the morphotropic phase boundary, when the titanium and zirconium atoms in the ceramic are uniformly distributed over the grains, as well as in the individual grains, and when the sintering temperature for the piezoceramic is as low as possible. The latter condition achieves stable and reproducible conditions by minimizing the evaporation of the lead oxide content from the ceramic during the sintering. These demands can only be met when extremely fine, chemically uniform and pure-phase PZT powders having a suitable stoichiometry are used for shaping the green compacts, which can subsequently be sintered at low temperature. 
     Numerous methods are known for producing PZT powders having the required properties. For example, powders can be produced chemically by co-precipitation, spraying reaction or sol-gel processes. These powders already contain all cations including lead. An optimally low sintering temperature is usually achieved by controlling the fineness of the particles. 
     A mixed oxide method is often used for practically producing a piezoceramic in commercial quantities. In this method, a mixture of lead oxide (PbO) dopant oxides, titanium dioxide (TiO2) and especially finely particulate zirconium oxide (ZrO2) is ground, dried and, typically, convened (calcined) into PZT powder at approximately 900 deg. C. Due to the different reaction behavior of TiO2 and ZrO2 with PbO, however, PZT powder particles arise having a Ti/Zr ratio from PbTiO3 (No zirconium) through PbZrO3 (No titanium) which is significantly scattered around a desired value. The powder must therefore be ground and mixed a second time. The homogeneity of the titanium/zirconium ratio which can be achieved by diffusion and grain growth in the sintering of this known powder during compression is limited by the sintering temperature, by particle size, as well as by the heterogeneity of the powder. The optimum piezoelectric material values of the sintered ceramic, or the optimum composition of the sintered ceramic with respect to the morphotropic phase boundary, are empirically set for each process on site, and may be possibly re-adjusted by a fine variation of the oxide mixture with respect to the Ti/Zr ratio. A reproducible production of PZT piezoceramics is thus possible by means of above mentioned processes. 
     Referring again to FIG. 3, in the first steps of the preferred embodiment of the present invention, a ceramic powder is combined  100  with an organic binder and pressed  102  into “green” shapes. The organic binding material used in the present process bonds the particles of ceramic powder together and enables formation of the required shape with desired solids content (i.e., ratio of ceramic powder to binding material). The organic binding material pyrolyzes, i.e. thermally decomposes, at an elevated temperature ranging generally from about 50 deg. C to below about 800 deg. C, and preferably from about 100 deg. C to about 500 deg. C. In non-oxidizing atmospheres, the binding material decomposes to elemental carbon and gaseous product of decomposition which vaporizes away. In an oxidizing atmosphere, the binding material decomposes to a gaseous oxidized product which vaporizes away. 
     The organic binding material is a thermoplastic material with a composition which can vary widely and which is well known in the art. Besides an organic polymeric binder it can include an organic plasticizer to impart flexibility to a green shape. The amount of plasticizer can vary widely depending largely on the particular binder used and the flexibility desired, but typically, it ranges up to about 50% by weight of the total organic content. The organic binding material may also be soluble in a volatile solvent. 
     Representative of useful organic binders are polyvinyl acetates, polyamides, polyvinyl acrylates, polymethacrylates, polyvinyl alcohols, polyvinyl butyrals, and polystyrenes. Representative of useful plasticizers are dioctyl phthalate, dibutyl phthalate, polyethylene glycol and glycerol trioleate. ordinarily, the organic binder has a molecular weight at least sufficient to make it retain its shape at room temperature and generally such a molecular weight ranges from about 20,000 to about 80,000. 
     The particular amount of organic binding material used in forming the mixture is determinable empirically and depends largely on the amount and distribution of solids desired in the resulting green shape. Generally, the organic binding material ranges from about 10% by volume to about 50% by volume of the solids content of the mixture in the green shape, and preferably constitutes about 15% to 25% by volume of the sinterable ceramic composition. 
     An oxidizing agent may be used when the green shape is to be sintered in a non-oxidizing atmosphere. The oxidizing agent should be used at least in an amount sufficient to react with the total amount of elemental carbon produced by pyrolysis of the organic binding material. For example, the actual amount of elemental carbon introduced by pyrolysis of the organic binding material can be determined by pyrolyzing the organic material alone under the same conditions used in the present cofiring and determining weight loss. Generally, the oxidizing agent ranges from about 0.5% by weight to about 5% by weight, and frequently from about 1% by weight to about 3% by weight, of the sinterable ceramic composition. 
     In carrying out the present process, the sinterable ceramic composition and organic binding material are admixed  100  to form a uniform or at least a substantially uniform mixture or suspension which is formed  102  into a sheet or other shape of desired thickness and solids content. A number of conventional techniques can be used to form the mixture  100  and resulting green shape  102 . Generally, the components are milled in an organic solvent in which the organic material is soluble or at least partially soluble to produce a castable mixture or suspension. Examples of suitable solvents are methyl ethyl ketone, toluene and alcohol. The mixture or suspension is then formed  102  into a sheet of desired thickness in a conventional manner, such as by doctor blading, or cast  102  into a desired shape by injection molding, extrusion, or pressing, and preferably hot pressing. The cast shape is then dried to evaporate the solvent therefrom to produce  102  the final green shape. 
     The particle size of the solids content of the mixture or suspension can vary widely depending largely on the particular substrate to be formed and is determinable empirically. The thickness of the present green shape can vary widely depending largely on its particular application. Generally, however, its thickness ranges from about 0.1 mm to about 10 mm. Preferably, the present green shape is of uniform or at least of substantially uniform thickness from about 1 mm to 6 mm. 
     In the present invention the green shape which is formed  102 , consists preferably of disk shaped wafers. Preferably two wafers are formed  102 , each wafer having two major opposing faces. The diameter of the wafer is generally greater than the thickness of the wafer and is generally at least four times the wafer&#39;s thickness. The wafers may be of equal or unequal thickness, depending on the final properties desired from the piezoelectric transformer. The wafers may be of unequal or preferably equal diameter. The wafers may also be made of dissimilar or preferably the same type of electrical ceramic materials. The green shape may also be of other shapes than disk-like wafers, such as in the shape of rectangular slabs. 
     The next step is to apply  104  metallization material to the green shapes. Metallization should be applied  104  to a major face of a green shape, and preferably to one face of each wafer. Metallization material is a metallization-forming material, i.e. during cofiring it forms the electrically conductive metal phase on the ceramic wafer. Generally, the metallization material is in the form of a paste or ink of the metal particles suspended in organic binder and solvent. Frequently, the metallization material also contains some glass frit or it may be mixed with some of the powder which formed the ceramic wafer. The glass or ceramic powder aid in the adherence of the metal to the ceramic wafer. Generally, the metal particles range in size from about 0.1 micron to about 20 microns and preferably from 2 to 5 microns. 
     The metallization material is a metal whose particles can be sintered together to produce a continuous electrically conductive phase during sintering  110  of the sinterable ceramic composition. Desirable metallization materials are materials that exhibit compatible thermal and mechanical properties with the electroactive ceramic. In particular, it is desirable to have a metallization material whose coefficient of linear expansion is close to that of the final sintered ceramic. Metallization that has a coefficient of linear expansion comparable to the final sintered ceramic is less likely to fracture or delaminate from the bonded ceramic. 
     Furthermore, the metal must be solid during sintering  110  to prevent migration of the metallization material into the ceramic during sintering  110 . Therefore, it is desirable that the metallization material have a high melting point, specifically, a melting point higher than the highest sintering temperature (usually around 1300 deg. C) of the ceramic. Metals which have lower melting points, such as aluminum (660 deg. C) and silver (962 deg. C), are thus not appropriate as metallization materials for electrical ceramics that require sintering temperatures above their melting points. 
     The properties of electroactive ceramics are typically optimized by heat treatments (sintering) at high temperatures (for example, 500 deg. C to 1300 deg. C). Many electrical ceramics, such as ceramic oxides require sintering in an oxidizing atmosphere. Many materials commonly used as electrodes are not suitable for use under high temperature and oxidizing conditions. The electrode material also should not deleteriously react with the ceramic substrate or the sintering atmosphere. As examples, aluminum electrodes would melt or react with the electrical ceramic oxide material; and silicides and polysilicon either react with the electrical ceramic at the higher temperatures or are oxidized at the surface in contact with the electrical ceramic oxide. 
     Moreover, if the oxide of an electrode metal has a high resistivity, reaction of the metallization material with the electrical ceramic oxide will create an interfacial dielectric layer of oxidized electrode material between the electrode and the electrical ceramic oxide. This may give rise to a capacitor in series with the electrical ceramic oxide, reducing the voltage drop experienced across the electrical ceramic oxide. Thus it is desirable that the metallization material not lose its conductivity due to reaction with oxygen or other ambients in the atmosphere or in the abutting ceramic layers. In the application of electroceramics as transformers, efficiency and the power factor are reduced as a result this loss. 
     Noble metals (e.g. platinum, palladium, and gold) may be used as electrode materials for multilayer piezoelectric devices. These noble metals have high melting points and are resistant to oxidation which helps to eliminate the problems associated with interfacial dielectric layers composed of the oxides of the electrode materials. Thus noble metals may be used as metallization for both oxide and non-oxide electroceramics. 
     Some other metals that are conductive are the platinum group metals (PGMs include Ruthenium, Rhodium, Iridium and Osmium). PGMs also form oxides that are conductive. Other conductive oxides of metals are Indium oxide and indium-tin oxide. These metals may be used as electrode materials for multilayer piezoelectric devices because they have high melting points, and because their oxides are conductive, they are resistant to the problems associated with interfacial dielectric layers composed of the oxides of the electrode materials. Thus, PGMs and their oxides may be used as conductors for both oxide and non-oxide electroceramics. 
     Some other metals readily oxidize in air at higher temperatures, forming nonconductive layers and thus are not suited to use as electrodes in oxide-containing electroceramics cofired in air. Among the metals that readily oxidize in air are zinc, copper and aluminum and particularly refractory metals (i.e., Tungsten @ 190 deg. C., Molybdenum @ 395 deg. C., Tantalum/Columbium @ 425 C.). Thus these metals are not appropriate as conductors for piezoelectric transformers cofired in an oxidizing atmosphere. These refractory metals however are desirable from the standpoint that they have good conductivity, high melting points, and a coefficient of linear expansion similar to that of final sintered electroceramics. The refractory metals may be used where the sintering atmosphere is slightly oxidizing with respect to the organic binder, but not oxidizing with respect to the metallization material, such as a hydrogen atmosphere with a high water vapor content. 
     The oxides of these metals may be appropriate in an alternate embodiment of the invention as intermediate dielectric layers located between the conductive layers in an oxide ceramic transformer. The refractory metals remain good conductors for non-oxide electrical ceramics, and in particular, the refractory metals have the advantages of having a high melting point and a coefficient of linear expansion similar to electroceramics. 
     The metallization material can be contacted  104  with the green shapes by a number of conventional techniques. These methods include Chemical Vapor Deposition (CVD), sputtering, and printing. Generally, the metallization is deposited or printed onto the electroceramic, and preferably it is screen printed thereon. 
     The shapes are then stacked  106  together, i.e. superimposed on each other, generally forming a sandwich. The stack can be laminated under a pressure and temperature determinable largely by its particular composition, but usually lower than about 100 deg. C., to form a laminated composite structure which is then cofired  108  and  110 . The term cofiring encompasses the application of heat  108  and  110  to the composite structure in a two part process. In the first part of the process, the temperature of the composite structure is raised  108  in order to cause the organic binder to burn off. In the second part of the cofiring process the temperature is again raised  110  in order to sinter the metallization and the ceramic. The final cofired structure is a sintered structure comprised of a sintered ceramic substrate and an adherent electrically conductive phase of metal or metal oxide between the ceramic layers. 
     The present cofiring process is carried out in an atmosphere in which the ceramic substrate and metal are inert or substantially inert, i.e. an atmosphere or vacuum which has no significant deleterious effect thereon. Specifically, for non-oxide ceramics, the atmosphere or vacuum should be nonoxidizing with respect to the metallization and the ceramic substrate. Representative of a useful atmosphere is dissociated ammonia, nitrogen, hydrogen, a noble gas and mixtures thereof. Preferably, a reducing atmosphere containing at least about 1% by volume of hydrogen, and more preferably at least about 5% by volume of hydrogen, is used to insure maintenance of sufficiently low oxygen partial pressure. Preferably, the atmosphere is at ambient pressure. 
     For oxide containing electroceramics, the sintering atmosphere is non-reducing, and is preferably air. However, where the metallization material oxidizes at higher temperatures, a slightly oxidizing atmosphere of up to 20 percent hydrogen in nitrogen with water vapor may be used (hydrogen to water ratio should be around 2.5). Preferably, the atmosphere is at ambient pressure. 
     Generally, during binder burn off  108 , in the firing temperature range up to about 500deg. C., a slower heating rate is desirable because of the larger amount of gas generated at these temperatures by the decomposition of the organic binding material. Typically, the heating rate for a sample of less than about 6 mm thickness can range from about 1 deg. C. per minute to about 8 deg. C. per minute up to 500 deg. C. 
     For non-oxide electrical ceramics, at a cofiring temperature of less than about 800 deg. C., the pyrolysis of the organic material is completed leaving a residue of elemental carbon. Generally, the amount of elemental carbon produced by pyrolysis is at least about 0.05% by volume, and usually at least about 0.4% by volume, of the substrate. When the cofiring temperature is increased  108  to a range of from about 800 deg. C. to about 1200 deg. C., but below the temperature at which closed porosity is initiated in the non-oxide ceramic substrate, the oxidizing agent reacts with the elemental carbon producing carbonaceous gases which vaporize away through the open porosity of the substrate thereby removing the elemental carbon from the substrate. 
     After the binder has burnt off  108 , the cofiring temperature is then increased  110  to the sintering temperature. The sintering temperature is that temperature at which the ceramic substrate densifies to produce a ceramic substrate having a decreased porosity. In the present cofiring, the rate of heating is determinable empirically and depends largely on the thickness of the sample and on furnace characteristics. After binder burnoff  108 , the rate at which the cofiring temperature is increased is about 200 deg. C. per hour. 
     The sintering temperature can vary widely depending largely on the particular ceramic composition, but generally it is above 800 deg. C. and usually ranges from about 900 deg. C. to about 1300 deg. C. For example, when firing PZT, upon reaching a sintering temperature from about 1240 deg. C. to 1300 deg. C., that temperature should be maintained for 1 to 8 hours. Below this temperature optimum density will not be achieved and above this temperature lead loss may become excessive and some melting may occur. The final porosity should be less than about 10% by volume, preferably less than about 5% by volume, and more preferably, less than about 1% by volume of the substrate. 
     During sintering  110 , the ceramic composition is liquid-phase sintered producing a ceramic substrate of desired density, and the metal particles are sintered together producing a continuous electrically conductive phase. During sintering  110 , a portion of the liquid phase which enables sintering of the ceramic migrates into the interstices between the sintering metal particles by capillarity resulting in a phase, usually a glassy phase, intermingled with the continuous phase of metal which aids in the adherence of the metal phase to the ceramic layers. 
     In order to produce a sufficiently densified ceramic, the composite structure must be sintered  110  in an appropriate atmosphere in order to enhance densification. For oxide based electrical ceramics, such as PZT, the sintering atmosphere should be substantially pure oxygen, although a positive oxygen pressure is unnecessary. A convenient way to achieve this atmosphere is to introduce pure oxygen into the open end of a tube furnace at a flow rate of about 150 cubic centimeters per minute. Sintering  110  should be carried out from 1240 deg. C. to 1300 deg. C. for 1 to 8 hours, below which optimum density will not be achieved and above which lead loss may become excessive and some melting may occur. It is preferred to sinter  110  at a temperature from 1280 deg. C. to 1300 deg. C. for 2 to 4 hours in order to achieve optimum density. 
     During sintering  110 , precautions should be exercised to avoid excessive lead loss by volatilization as such lead loss may be significant in shifting the composition outside the range in which optimum piezoelectric properties have been observed. For example, covering the pressed part with powder of the same composition, adding a compensatory excess of lead to the starting composition, carrying out sintering  110  in a sealed container, or a combination of one or more of these steps are appropriate precautions. 
     Upon completion of the cofiring  110 , the resulting structure is allowed to cool  112 , preferably to ambient temperature. The rate of cooling  112  can vary, but it should have no significant deleterious effect on the structure, i.e., should not cause thermal shock or cracking. Preferably, it is furnace cooled  112  to ambient temperature. The final ceramic should have a porosity of less than about 10% by volume, preferably less than about 5% by volume, more preferably less than 1% by volume, and most preferably, pore-free, i.e., fully dense. 
     Upon completion of the cofiring  110 , and more preferably upon completion of cooling  112  the sintered ceramic, exterior electrodes  76  and  78  may be applied  114 . The exterior electrodes  76  and  78  are deposited on the exterior faces of the ceramic wafers  70  and  72 . Because these exterior electrodes  76  and  78  do not undergo the cofiring process  108  and  110 , they are not required to withstand oxidation at high temperatures. Thus these electrodes  76  and  78  may be made of any conventional electrode material such as aluminum or silver. These exterior electrodes  76  and  78  may be applied  114  by any conventional means such as by sputtering, CVD, thin foil adhesion, or preferably by electroplating the exterior faces of the sintered ceramic. Optionally, the electrode materials  76  and  78  may be deposited  104  on both faces of the green ceramic and cofired  108  and  110  with the green shape to produce both the interior  74  and exterior electrodes  76  and  78 . 
     Upon completion of applying  114  the external electrodes, the sintered ceramic is then polarized  116 , preferably in the thickness direction (i.e. normal to the major faces transformer). Polarization should occur simultaneously to both ceramic layers  70  and  72  rather than one at a time, because dimensional shrinkage of a ceramic layer  70  due to the polarizing electric field may delaminate one ceramic layer  70  from the other ceramic layer  72 . Polarizing  116  may be accomplished by placing the sintered ceramic on a grounded, metallic, surface and contacting it with an electrically charged metal brush (not shown). Polarization  116  of the device should occur with the device submerged in oil, such as peanut oil or silicone oil, to prevent arcing across the electrodes under a high intensity electric field. The temperature of the ceramic should also come into equilibrium with the temperature of the oil (about 80 deg. C to 120 deg. C) to prevent damage to the ceramic. As the sintered ceramic comes into contact with the metal brush, the metal brush is electrically charged by a power supply, and the bottom facing exterior electrode  78  on the sintered ceramic is electrically conducted to the (grounded) surface, and the brush electrically conducts to the upward facing exterior electrode  76  of the sintered ceramic. The high voltage charge of the metal brush (e.g. 12 to 15 Kilovolts/cm) polarizes  116  the ceramic layers  70  and  72  of the sintered ceramic transformer  2 . To prevent arcing as the electrode  76  comes into close proximity with the metal brush, the power supply is only turned on after the electrode  76  establishes contact with the metal brush. This method of polarizing  116  produces two ceramic layers  70  and  72  polarized  116  in the same direction (i.e., 70 +/−, 72 +/−). It may be desirable to polarize the ceramic layers  70  and  72  in different directions with respect to each other (i.e., 70 +/−, 72 −/+). For polarizing  116  in this manner, the center electrode  74  is grounded and metal brushes contact the outer electrodes  76  and  78 . 
     A piezoelectric transformer  2  constructed in accordance with the preceding description comprises a pair of piezoelectric ceramic wafers  70  and  72  which are intimately bonded to each other along one of each of their major faces by an internal electrode  74  formed by the metallization layer  74 . Electric terminals  80 ,  82  and  84  are connected (e.g. by wire and solder, or other common means) to an exposed surface of the electrodes  76 ,  78  and  74  respectively. 
     Referring to FIG.  4 : When a primary (i.e. input) voltage V 1  is applied across terminals  82  and  84  connected to the electrodes  78  and  74  of the first ceramic wafer  72 , the first ceramic wafer  72  will piezoelectrically generate an extensional stress commensurate with the magnitude of the input voltage V 1 , the piezoelectric properties of the wafer  72  material, the size and geometry of the wafer  72  material, and the elasticity of the electrodes  78  and  74  which are bonded to the first wafer  72 . The extensional stress which is generated by the input voltage V 1  causes the first ceramic wafer  72  to be radially strained. 
     Because the first ceramic wafer  72  is securely bonded to the second ceramic wafer  70  (i.e., by internal electrode  74 ), any radial strain (and bending) of the first ceramic wafer  72  will result in a radial strain (of the same magnitude and direction) in the second ceramic wafer  70 . The radial strain (and bending) of the second piezoelectric ceramic wafer  70  generates a voltage potential V 2  across the two electrodes  74  and  76  of the second ceramic wafer  70 . The electric terminals  84  and  80  may be electrically connected to corresponding electrodes  74  and  76  of the second ceramic wafer  70 . The magnitude of the piezoelectrically generated voltage V 2  between the two electrodes  74  and  76  of the second ceramic wafer  70  depends upon the piezoelectric properties of the wafer  70  material, the size, geometry and poling of the wafer  70  material. 
     Thus, by applying a first voltage V 1  across the electrodes  78  and  74  of the first ceramic wafer  72 , the first ceramic wafer  72  is caused to radially strain, which, in turn, causes the second ceramic wafer  70  to radially strain a like amount, which, in turn produces a second voltage potential V 2  between the electrodes  74  and  76  of the second ceramic wafer  70 . 
     The ratio of the first voltage V 1  to the second voltage V 2  is a function of the piezoelectric properties of the wafer  70  and  72 , the size and geometry of the wafers  70  and  72  material, the elasticity of the other materials of the other laminate layers (i.e., internal electrode  74  and external electrodes  76  and  78 ) and the poling characteristics of the two ceramic wafers  70  and  72 . 
     As shown in FIG. 4, in the preferred embodiment of the invention, in the piezoelectric transformer  2 , the facing surfaces of the first ceramic wafer  72  and second ceramic wafer  70 , respectively, are electrically connected to a common electric terminal  84  connected to the metallization  74  layer. 
     Referring now to FIG.  5 : In an alternative embodiment of the transformer  3 , the corresponding facing metallized  74  surfaces of two ceramic wafers  70  and  72  are electrically insulated from each other, (for example by a dielectric layer  67  such as another ceramic), and connected to corresponding terminals. In this embodiment of a piezoelectric transformer  3 , the facing surfaces of the first ceramic wafer  72  and second ceramic wafer  70 , respectively, each have an internal electrode  74  (which are separated by the dielectric layer  67 ). Each internal electrode  74  is electrically connected to a common electric terminal  84  at the exposed surface of the internal electrode  74 . A piezoelectric transformer  3  constructed in accordance with this modification of the invention may be used in an electric circuit to electrically protect electrical components “downstream” from the transformer  3  from damage from high current discontinuities “upstream” of the transformer  3 . 
     Referring now to FIG.  6 : In an alternative embodiment of the transformer  4 , the corresponding facing metallized  74  surfaces of two ceramic wafers  70  and  72  are electrically insulated from each other, (for example by a dielectric layer  67 ), and connected to different corresponding terminals. In this embodiment of a piezoelectric transformer  4 , the facing surfaces of the first ceramic wafer  72  and second ceramic wafer  70 , respectively, each have an internal electrode  74  (which are separated by the dielectric layer  67 ). Each internal electrode  74  is electrically connected to a separate electric terminal  86  and  88  at the exposed surface of the internal electrode  74 . In this embodiment of the transformer  4 , the two piezoelectric ceramic wafers  70  and  72  are completely electrically isolated from each other. A transformer  4  constructed in accordance with this modification of the invention may be used in an electric circuit to electrically protect electrical components “downstream” from the transformer  4  from damage from high current discontinuities “upstream” of the transformer  4 . 
     While the above description contains many specificities, these should not be construed as limitations on the scope of the invention, but rather as an exemplification of one preferred embodiment thereof. Many other variations are possible, for example: 
     The two ceramic wafers  70  and  72  may be constructed of either similar or dissimilar piezoelectric materials which may either have identical or dissimilar piezoelectric coefficients; 
     The two ceramic wafers  70  and  72  may either be of equal or unequal thicknesses; 
     The ceramic wafers need not be disk shaped but may also be of a rectangular or other shape; 
     The ceramic wafers need not be flat but may be curved or dome shaped; 
     There may be more than two ceramic wafers; 
     Metallization may be used on more than one face of a ceramic wafer and can be used for both internal and external electrodes; 
     Metallization may be applied on only one or both facing surfaces of ceramic wafers; 
     Electrical connections need not be made solely on the exposed surface of the internal electrode but may be connected with through holes or vias; 
     External electrodes may by applied by any metal deposition technique including using an adhesive to attach one or both external electrodes; 
     The green ceramic wafers may be formed by any technique for making green shapes including doctor blading, extrusion, injection molding, casting, pressing, hot pressing or the like; 
     Sintering/cofiring may be conducted in an oven, a crucible, on a plate, in an autoclave, by conductive heating in a hot press or the like manner of heating; 
     Sintering/cofiring may be conducted in a reducing, oxidizing or neutral atmosphere depending on the desired reaction of the atmosphere with the ceramic or the metallization material; 
     Sintering/cofiring need not be conducted in a vacuum, or at a atmospheric pressure, but may be conducted at any pressure; 
     Binder burn-off and sintering the ceramic/metallization may be conducted in different atmospheres, at different pressures and by different heating mechanisms; 
     Accordingly, the scope of the invention should be determined not by the embodiment illustrated, but by the appended claims and their legal equivalents.