Patent Application
20080171176
The present invention relates to the crystalline ferroelectric microwave components and device structures which are electronically controllable or tunable. The microwave components contains a flexible, lightweight, and adaptable metal foil substrate and a dielectric thin film having a non-linear dependence on an applied electric field. The microwave components are suitable for frequency-tunable microwave applications, such as microstrip patch ferroelectric antenna, thin film ferroelectric microwave phase shifters, tunable filters for wireless communications, and hybrid ferroelectric/superconducting microwave circuits.
High frequency microwave devices are extensively used in mobile communications systems. These devices employ planar circuits consisting of a conductor deposited on a film which exhibits an electric-field-dependent dielectric constant. Ferroelectric materials are non-linear dielectrics that display an electric-field-dependent dielectric constant. This, in turn can be employed in frequency-tunable microwave circuits. The crucial parameters required for tunable microwave devices include the degree of change in dielectric constant as a function of applied electric field, as well as dielectric loss at microwave frequencies. Ferroelectric thin-film devices are attractive in various applications requiring high tuning speed, small size, low power consumption, and low weight. For a tunable structure, a figure of merit K is defined as
K=(C0−CV)/(C0 tan δ0)
where C0 and CV are the capacitance values at zero and maximum dc bias voltage, and tan δ0 is the loss tangent with no bias.
Ferroelectric materials, such as barium strontium titanates, (BaSr)TiO3, for microwave device applications have been reported in the literature. See, for instance, Zhu et al, “Recent Progress of (BaSr)TiO3 Thin Films for Tunable Microwave Devices”, J. Electron. Mater., vol. 32 (10), pp. 1125-1134, 2003. Such films demonstrate excellent dielectric properties and large electric-field dielectric tunability which makes them especially suitable for tunable microwave components and devices. The use of ferroelectrics in the area of communications is desired in order to more efficiently manufacture electronically scanned antennas (ESA).
The thin film components of the invention is useful in frequency-tunable microwave applications, such as microstrip patch ferroelectric antennas, thin film ferroelectric microwave phase shifters, tunable filters for wireless communications and hybrid ferroelectric/superconducting microwave circuits. The ferroelectric thin film composites have particular applicability in circuits employing voltage-controlled capacitance and variable wave velocity. It is the flexibility of the substrate which permits the application of different voltages onto the component such that different capacitance values may be rendered.
The thin film composites contain a flexible metallic substrate, a first ferroelectric thin film layer and a patterned thin metal layer. An optional barrier layer rests between the flexible metallic substrate and ferroelectric thin film layer.
The component is prepared by depositing onto the flexible metallic substrate a precursor composition using sol-gel, sputtering, pulsed laser deposition (PLD), molecular beam epitaxy (MBE) and various printing methods. The resultant is a tunable dielectric which is capable of changing frequency at selected electric fields.
The ferroelectric layer may be composed of one or more dielectric layers. The total thickness of the ferroelectric thin film layer is between from about 50 nm to about 900 mn.
The substrate is a flexible metallic foil which allows the composite to conform and maintain its integrity under external conditions. Suitable flexible metallic foils include nickel alloys, aluminum, brass, titanium, nickel-coated copper, platinum, stainless steel, platinum-plated silicon and nickel-coated copper foils.
In order to more fully understand the drawings referred to in the detailed description of the present invention, a brief description of each drawing is presented, in which
The thin film ferroelectric devices, set forth in
Among these methods, sol-gel is especially preferred since deposition may occur at sufficiently low temperatures. Suitable low temperature sol-gel coating techniques include spin coating, dip coating, spray coating, meniscus coating, flow coating, physical vapor deposition (PVD), and metal organic chemical vapor deposition (MOCVD) and various printing methods. Deposition of the precursor using low temperatures sol-gel processes is especially advantageous with mismatched structures since the effect of thermal expansion mismatch is minimized. In addition, in comparison with other methods, sol-gel processing is relatively inexpensive and facilitates fast sampling of materials. Other deposition techniques may be used which promote uniformity especially those which minimize defect concentration and residual stresses.
The precursor compositions may be deposited onto the flexible metallic substrate by sol-gel techniques to form a tunable dielectric wherein the substrate serves as a bottom electrode.
The ferroelectric thin film precursor composition contains an organic solvent and organometallic components capable of forming the desired inorganic oxide dielectric. In a preferred embodiment, the mixture is mixed at approximately 110° C. for about 90 minutes.
The barrier precursor composition contains an organic solvent and organometallic compounds. After deposition, the composition is heated, prior to applying the precursor for the ferroelectric thin film layer, to remove the organic components and to render a dense buffer layer on the substrate. Typically, the composition is baked at a temperature from about 100° C. to about 450° C. and for a duration of about one to ten minutes. The organometallic compounds in the buffer precursor composition form, upon heating, inorganic oxides which, while exhibiting dielectric properties, provide improved attachment and bonding of the first dielectric thin film layer onto the substrate. The inorganic oxides of the buffer layer may be those recognized in the art. The optional buffer layer has a thickness between from about 40 nm to about 300 nm. The buffer layer may serve as a barrier against mechanical stress and failure from the substrate.
The ferroelectric layer may be composed of one or more dielectric layers wherein each layer is deposited and heated prior to deposition of the next layer. Thus, the ferroelectric layer, as that term is used herein, may consist of multiple layers. The precursor composition for each of the layers is preferably the same. When composed of multiple layers, the ferroelectric layers may be in a regular or irregular superlattice structure. The total thickness of the ferroelectric thin film layer is between from about 50 nm to about 900 nm, preferably between from about 50 nm to about 300 nm. The total thickness of the ferroelectric thin film layer is generally greater than the thickness of the barrier layer, when present. Thickness may be controlled by rotation rate and the viscosity of the precursor composition.
The precursor composition of the barrier layer and/or ferroelectric thin film layer may further contain a stabilizing amount of a glycol, such as polyethylene glycol.
The resulting product is annealed and a patterned thin metal layer may then be formed. The onset of the ferroelectric transition depends on the annealing temperature. Thus, the product is annealed at elevated temperature until crystallization. Generally, the annealing conditions will be selected to increase the grain size of the substrate comprising the thin film composite as well as to induce a textured condition in the substrate. Annealing may proceed in an oven at a temperature of from about 500° C. to about 850° C. for approximately one hour or by rapid thermal annealing using quartz halogen lamps, laser-assisted annealing using, for example, an excimer or carbon dioxide laser, or using electron beam annealing. Subsequent annealing, in turn, enhances the texture and degree of crystallinity of the dielectric thin film. The resulting porous structure provides an increased surface area and thus improves adhesion. Annealing further promotes film crystallinity.
The inorganic oxide of the optional barrier layer and ferroelectric thin film layer are typically composed of the same elements although the ratio of the elements may be different. Each of the film layers is preferably polycrystalline or nanocrystalline film.
Exemplary as the inorganic oxide of either the barrier or ferroelectric thin film layer is lead lanthanide titanate, lead titanate, lead zirconate, lead magnesium niobate, barium titanate, lead zirconate titanate, barium strontium titanate, lanthanum-modified lead zirconate titanate, bismuth zinc niobate and bismuth strontium tantalite. Preferred oxides are lead zirconate titanate, barium strontium titanate, lanthanum-modified lead zirconate titanate, bismuth zinc niobate and bismuth strontium tantalite.
Especially preferred are those titanates of the formula PbZr1−x TixO3 family with 0<x<1; preferred are those of the formula PbZrxTixO3 wherein x is between from about 0.30 to about 0.70, more preferably between from about 0.35 to about 0.65. Especially preferred as barium strontium titanates are those of the formula (Ba1−xSrx)TiO3 wherein 0<x<1.0, most preferably wherein x is between from about 0.1 to about 0.9, most preferably 0.3 to about 0.7. One preferred embodiment is represented by the formula Ba0.5Sr0.5TiO3. Especially preferred as lanthanum-modified lead zirconate titanates are those of the formula PbyLaz(Zr1−xTix)O3 wherein x is from about 0.30 to about 0.70, preferably between from about 0.35 to about 0.65, y is from 0.95 to about 1.25, and z is from about 0 to about 0.15. Further preferred as bismuth zinc niobates are those of the formula Bi3xZn2(1−x)Nb2−x-O7 wherein x is from about 0.40 to about 0.75; and bismuth strontium tantalates of the formula SrxBiyTa2O5+x+3y/2 wherein x is from about 0.50 to about 1.0 and y is from about 1.9 to about 2.5.
The substrate is a flexible metallic foil which allows the composite to conform and maintain its integrity under external conditions. The metallic foil substrate is sufficiently thin to allow it to be shaped by bending or rolling according to specific geometrical requirements for targeted device constructions. Suitable flexible metallic foils include nickel alloys, aluminum, brass, titanium, nickel-coated copper, platinum, stainless steel, platinum-plated silicon and nickel-coated copper foils. Most preferable, the thickness of the metallic foil substrate is in the range between from about 10 to about 300 microns. The substrate may be a flat surface, textured surface or macroporous surface. The flexibility of the substrate permits the application of different voltages onto the component such that different capacitance values may be rendered. The ability to exhibit different capacitance values in electrical circuits causes the creation of different resonance frequencies.
The constituency of the organometallic components in the precursor composition is dependent on the desired ferroelectric film. Typically the titanium, niobium and tantalum elements of the ferroelectric originate from a metal alkoxide, such as titanium isopropoxide. The remaining metals are typically derived from metal acetates. For instance, the precursor solution of the barrier layer may be prepared by using starting materials containing the requisite amounts of barium, strontium, lead, and lanthanum precursors, such as barium acetate, strontium acetate, lead acetate, lanthanum isopropoxide and titanium isopropoxide.
The organic solvent used in the precursor compositions is typically a glycol, such as ethylene glycol and propylene glycol, or an alkanol, such as ethanol, isopropyl alcohol, methanol and n-butanol, or weak organic acids, such as acetic acid.
As an exemplary of a process within the procedure set forth in
Structures derived from the composites of the invention include microwave components and devices such as non-linear dielectric thin film composites for frequency-tunable microwave applications, such as microstrip patch ferroelectric antennas, thin film ferroelectric microwave phase shifters, tunable filters for wireless communications and hybrid ferroelectric/superconducting microwave circuits. The ferroelectric thin-film layer of the composite affords a large field-dependent dielectric constant (necessary for compact tunable circuits), fast field response (for facilitating fast switching speeds), and high breakdown fields. As such, the ferroelectric thin films have particular applicability in circuits employing voltage-controlled capacitance (e.g., voltage-controlled oscillators, tunable filters, and phase shifters) and variable wave velocity (e.g., distributed phase shifters, delay lines). The structure is flexible and thus easy to integrate into different shaped objects including structures which do not exhibit planar flat surfaces.
The resulting components are tunable or controllable such that a particular wave range, wavelength or wave direction may be changed by application of an electric field.
The use of ferroelectric materials as phase shifters present substantial advantages towards inexpensive fabrication possibilities on a single substrate. Such fabricated ferroelectric thin films on a single substrate have particular applicability in the case of phased arrays which employ hundreds of radiating elements and a large number of phase shift elements. In such cases, cuts are related to the number of elements and active electronic devices, such as phase shifters. In phased array antennas, phase shifters and delay lines, employment of voltage-controlled modulation of the dielectric constant and time delay in delay lines may be employed to phase delay microwave signals transmitted (or received) from the separate radiative elements of the array.
In a preferred mode, the composites of the invention are formed on a metal foil substrate are useful as microstrip patch ferroelectric antenna for ground plane.
The value of merit K, and hence the resonance frequency, is controlled by applying an electric field across the ferroelectric film. For this purpose, a controllable DC bias potential is applied between the microstrip patch and the ground plane. The resulting structure facilitates the application of a controllable voltage across the dielectric layer, thus controlling a dielectric constant of said dielectric material. For isolation of the DC bias source from the radio-frequency signal, the DC bias is fed in via a high-impedance microstrip transmission line with one end connected to a corner of the patch and the other end terminated in a quarter-wave radial stub (the quarter-wavelength radius would be chosen for a frequency near the middle of the desired radiation-frequency range). A wire delivers the bias voltage to a radio-frequency virtual-short-circuit location on the transmission line so that the impedance is not perturbed.
A multimode patch antenna may be designed to resonate at an odd sub-multiple of possibly widely separated desired operating frequencies. By using a combination of (1) varying the DC bias voltage to vary the dielectric constant of the ferroelectric film and (2) selection of the desired harmonic frequency, one can effectively achieve tuning over a very wide frequency range.
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/IB2005/000662 | 3/15/2005 | WO | 00 | 10/9/2007 |
| Number | Date | Country | |
|---|---|---|---|
| 60553159 | Mar 2004 | US |
