GLASS CERAMIC COMPOSITES

Abstract: A method for joining glass ceramic surfaces to each other and/or other types of surfaces using a silicate liquid is disclosed. The products are suitable for use as, <i>e.g.</i> mirror blanks or microlithography stages, at low temperatures. Component pieces are polished then joined at low temperature using a silicate-containing joining liquid. Assembly is then performed in such a way that the joining liquid forms an interface between each component. After a period of low or slightly elevated temperature curing, rigid joints are formed throughout and the composite is dimensionally, vibrationally, and temperature stable and can withstand tensile stresses > 4000 psi. The room-temperature cured composite can be heat treated using a slow, systematic temperature increase to dehydrate the joints. A sealing coating may optionally be provided to prevent excess dried joining liquid from flaking off the formed joint.

Description: Glass Ceramic Composites Background 5 I. Field of the Invention The invention relates to the field of glass ceramic composite structures and methods for forming composite glass ceramic structures using a low temperature joining process. II. Description of the Prior Art 0 Glass ceramics, which generally consist of an inorganic, non-porous material having a crystalline phase and a glassy phase, are known for specialized applications. Such glass ceramics are manufactured by selecting suitable raw materials, melting, refining, homogenizing, and then hot forming the material into a glassy blank. After the glassy blank is cooled and annealed, a temperature .5 treatment follows whereby the glassy blank is transformed into a glass ceramic by controlled volume crystallization (ceramization). Ceramization is a two-step process; nuclei are formed within the glass at one temperature, and then grown at a higher temperature. The dual structure of the glass ceramic material can impart very special properties, including a very low coefficient of thermal !0 expansion (CTE). One preferred material, Zerodur® (available from Schott Glass Technologies, Duryea, Pennsylvania) contains about 65-80 weight percent crystalline phase with a high quartz structure, which imparts a negative linear thermal expansion. The remaining glassy phase (which surrounds the crystals) has a positive thermal expansion. The resulting behavior from the negative-CTE crystalline phase and the positive-CTE glassy phase is a material with an extremely low CTE. Glass ceramics are useful in a wide variety of applications, such as mirror substrates for astronomical telescopes; mirror substrates for X-ray telescopes in satellites, optical elements for comet probes, weather satellites, and microUthography; frames and mirrors for ring-laser gyroscopes; distance gauges in laser resonators; measurement rods as standards for precision measurement technology, and other uses where very low CTE is important. Large segments of monolithic glass ceramic are often used for many of the applications listed above. However, these large segments of monolithic glass ceramic are often very massive. For instance, larger astronomical telescopes can contain mirrors that exceed 3.6 meters, and the appropriate glass ceramic for use in such telescopes can exceed several tons. Thus, there is a need to develop light- weighted glass ceramic materials to overcome the problems associated with the massive nature of large monolithic segments of glass ceramic. Various joining methods for optical materials are known; e.g. heat fusion, or frit bonding, however, none provides a low-temperature solution such as is provided for in the present invention. The known prior art for fabricating light-weighted blanks (i.e. heat fusion, frit bonding) suffers from several drawbacks. For example, pressure and temperature are typically required to form strong joints at high temperature. Developing loading/ unloading fixtures for operation at T>600°C is complex and expensive. Further, heat fusion and frit bonding processes are conducted at temperatures near or above the glass transition temperature (T g ) of the starting material (i.e., glassy Zerodur®, or ULE). The viscosity of glass is sufficiently low at these temperatures, such that limited flow (deformation) can occur. This deformation can cause gross dimensional changes, which can yield a defective mirror blank. Additionally, large, high temperature furnaces (up to 2.0 m in diameter) with stringent thermal tolerances are required for heat fusion and frit bonding. Such furnaces must be custom-made and are often very expensive. Furthermore, glassy Zerodur® shrinks by approximately 3% during ceramization. This shrinkage can cause joint stresses that result in deformation and/ or catastrophic failure of the mirror blank during joining. Yet another difficulty encountered in the prior art is that light-weighted mirror blanks can fail during high temperature joining when thermally induced stresses form at the joint interfaces (especially during cooling to room temperature). Such joint failure results in a 100% loss after a tremendous amount of value has been added to the mirror blank (i.e., machining, polishing, water-jet cutting, assembly, high temperature fixturing, etc.). A solution to this problem is needed, to allow for the low-temperature joining of fabricated mirror blanks in a step-wise manner. Brief Description of the Drawings Figure 1A is a perspective view of a preferred embodiment of a lightweight mirror blank according to the present invention. Figure IB is a top plan view of a preferred embodiment of a Hghtweight mirror blank according to the present invention. Figure IC is a side view of a preferred embodiment of a lightweight mirror blank according to the present invention. Figure ID is a perspective view of a support element of a preferred embodiment of a lightweight mirror blank according to the present invention. Figure 2 is a diagrammatic representation of the molecular structure of a surface of a glass ceramic material suitable for joining according to the present invention. Figure 3 is a diagrammatic representation of the molecular structure of a joined glass ceramic material according to the present invention. Figure 4 is a graphical representation of the average flexural strength of monolithic Zerodur® compared to various joined Zerodur® components. Figure 5 is a graphical representation of the average CTE of joined Zerodur® rods. Figure 6 is a diagrammatic representation of the vapor pressure build up between bulk Zerodur® blocks. Figure 7 is a perspective view of a joined flexural sample. Figure 8 is a perspective view of a joined CTE rod. Summary of Invention The present invention relates to a low-temperature process for the fabrication of Hghtweight composite glass ceramic structures, comprised, e.g., of a pluraHty (e.g., two or more) of glass ceramic components, said glass ceramic components each being poHshed sufficiently to form at least one joining surface on each component, providing a siHcate-containing joining Hquid to at least one of the joining surfaces, bringing the joining surfaces of the pluraHty of glass components together to form a joint, and allowing the joint to cure for a period of time at ambient temperature, whereby a cured joint is formed between said pluraHty of glass components. It also relates to a glass ceramic composite, comprising a pluraHty of glass ceramic components, said components being rigidly connected by a siHcate-containing layer formed by curing a siHcate- containing liquid between the glass ceramic components. The composites are preferably dehydrated by a carefully controHed dehydration process. For example, a low-temperature process for the fabrication of lightweight composite glass ceramic structures, comprises: providing a plurality of glass ceramic components, said glass ceramic components each being poHshed to form at least one joining surface on each component, providing a siHcate-containing joining Hquid to at least one of the joining surfaces, bringing the joining surfaces of the plurality of glass components together to form a joint, aUowing the joint to cure for a period of time of at least 20 hours at a temperature of at least 20 degrees C, whereby a cured joint is formed between said plurality of glass components, and dehydrating the cured joint gradually by raising the temperature slowly and maintaining an elevated temperature below the glass transition temperature of the glass ceramic for at least 20 hours. This invention also relates to: A glass ceramic composite, comprising: a pluraHty of glass ceramic components, said components being rigidly connected by a silicate-containing layer formed by curing a siHcate-containing liquid between the glass ceramic components at a temperature of at least 20 degrees C for at least 20 hours; A mirror blank suitable for use in space or flight appHcations comprising a pluraHty of glass ceramic components joined by a silicate-containing Hquid and cured at a temperature of at least 20 degrees C; A composite glass ceramic structure suitable for use as a microHthography stage comprising a plurality of glass ceramic components joined by a siHcate- containing Hquid and cured at a temperature of at least 20 degrees C; A method of joining lightweight composite glass ceramic surfaces comprising applying to at least one of said surfaces a silicate-containing solution and curing for an extended period at a sHghtly elevated temperature above room temperature; and A light weight glass-ceramic mirror blank, comprising: a face plate which is circular in shape, a back plate which corresponds in shape and size to the face plate, a pluraHty of support elements located between said face and back plates, said plurality of supporting elements forming a latticework said latticework and face plate and back plate defining a pluraHty of ceUs, said cells each being provided with a ventilation aperture or being open to the environment, said face plate, pluraHty of supporting elements, and back plate being joined by a siHcate-containing Hquid in a pluraHty of joining steps to form a plurality of joints, and at each step, the joint cured at a temperature of at least 20 degrees C for a period of at least 20 hours. A light- weighted mirror blank according to the present invention can be comprised of thin (preferably <5cm) face and back-plates that are fused, joined or bonded to a Hght-weighted core. Figures 1A, IB, IC, and ID iUustrate some of the separate components that may comprise a light-weighted Zerodur® mirror blank. While much of the description herein is in terms of the preferred Zerodur® material and mirror blanks, any glass ceramic material in general for any appHcation is included in the invention. With reference to Figure 1A, the face 10 and back plates 14 may be flat or curved sheets of Zerodur® that are polished on both sides. The light-weighted core may be a poHshed honeycomb-shaped component, which may be prepared by water-jet cutting segments from a soHd slab of Zerodur®. It may also comprise supporting elements 12 arranged to support and space the face and back plates. After assembly and fusion, a light-weighted mirror blank often has an overall mass/ volume ratio that can be 30% of that for a standard (soHd) Zerodur® blank, or even as low as 5 or 10% or even lower. Figure IB is a top view illustrating a preferred arrangement including the supporting elements 16 and ventilation holes 18. Figure ID illustrates a preferred way of joining two supporting elements 20, 22 using corresponding slots 24, 26. Optionally, the slots may be prepared with poHshed mating surfaces and joined according to the present invention. Applicants have developed a novel method for fabricating composites, especially light-weighted glass ceramic mirror blanks and microHthography stages, at low temperatures. By low temperatures, as used herein, is meant temperatures generaUy under the glass transition temperature of the glass ceramic. Temperatures under 500°C may be suitable for practice of the invention, more preferably below 140°C, even more preferably below 130°C, most preferably, the temperature is <120°C. The Hght-weighted glass ceramic mirror blanks are intended for appHcations where dimensional stabiHty, adequate strength and low mass/ volume are critical. Such appHcations include, but are not limited to, optical systems intended for space flight and airborne based applications such as satellites, navigation systems, and remote sensing, land-based systems, and precision structures such as microlithography stages. The light-weighted structures according to the present invention should be rigid when compared to a monolithic piece of glass ceramic that the structures are replacing. By "rigid" is meant having essentially the same vibrational characteristics as the monolithic piece, being vibrationaHy, thermaUy, and otherwise dimensionaUy stable so as to have essentiaHy indistinguishable opto- mechanical and thermo-optical characteristics from those of the monoHthic piece of glass ceramic. In a preferred embodiment, a low temperature joining technique is provided which allows light-weighted mirror blanks to be fabricated in a step- wise manner. In a preferred embodiment, a poHshed face-plate, back-plate and light- weighted core are first prepared from the commerciaUy available glass ceramic known as Zerodur®. The poHshed components are cleaned in various aqueous and non- aqueous solutions before being dried and placed in a clean room environment. A smaU volume of an aqueous based, silica-containing, joining Hquid is applied to the polished joining surfaces of each component. Assembly is then performed in such a way that the joining Hquid forms an interface between each component (i.e., between the faceplate and the Hght-weighted core). After a period of room temperature curing, rigid joints are formed throughout the light- weighted mirror blank, which can withstand tensile stresses >4000 psi. Furthermore, the dimensional stabiHty of the joined mirror blank is similar to that of pure, monolithic Zerodur® (i.e., the coefficient of thermal expansion of the blank is < 75 ppb/K, is unaffected by the joining, and is the same as the monoHthic glass ceramic that is being replaced). Such room-temperature-cured mirror blanks are then preferably heated to temperatures ranging from 60 to 120°C to promote joint dehydration and accelerate the curing process. In a particularly preferred embodiment, the joints are subjected to an extended duration of sHght temperature increase to dehydrate the joints. The removal of water from the joints over an extended period of time dramatically increases the strength, reHabiHty, and rigidity of the structures according to the present invention over the strength, reHabiHty, and rigidity of joints that are quickly dehydrated (e.g. by microwave). Preferable temperatures for the extended duration dehydration include from 20-50 degrees C for at least 20 hours, more preferably from 30-40 degrees C for at least 20 hours up to three weeks. Several advantages arise out of the novel low-temperature joining process. First, a Hght-weighted mirror may now be constructed piece by piece, thus eliminating some of the risk associated with the high temperature processes. During high temperature processing the entire mirror blank could deform during heating or fracture during cooling, with no indication until furnace unloading. Second, a drying furnace capable of temperatures up to «120°C may be required for low-temperature joining. Such low temperature drying furnaces are commerciaUy available and much less expensive than high temperature furnaces. Third, no material deformation occurs, since low temperature joining is conducted at temperatures well below the T g , where glass ceramics are elastic solids. Fourth, fuHy ceramized glass ceramics are utilized for low temperature joining. This eliminates the problems associated with the shrinkage that occurs when the glass is converted to a glass ceramic during heat fusion. Fifth, pressure is not typically required for low temperature joining. Thus, no compHcated loading/ unloading fixtures are necessary. These and other advantages will become apparent to one of skill in the art having regard for this disclosure. A lightweight mirror blank represents a substantial investment of time and materials, which makes the mirror blank very expensive. If a defect arises or a catastrophic failure occurs within the unit during high temperature bonding (e.g. heat fusion or frit bonding), the entire value-added process is a loss and the process must start anew. The applicants have developed a novel process which provides for the component by component assembly of large, light-weighted structures, and may be accompHshed at low temperatures (i.e. weH below the Tg of typical alkali-alumino silicate glasses, <500°C). Glass ceramics that are joined according to the instant invention are first prepared by selecting the monoHthic pieces to be fabricated into a finished composite structure. Various elements, e.g. mirror components, face plates, back plates, and structural connections are fabricated and sized to yield a composite, light-weighted structure which has a low thermal expansion. A Hght-weighted mirror blank, for example, as used herein, is a physical structure onto which a reflective coating may by applied to form a functional mirror. Mirrors are typicaHy used during flight or space applications where remote sensing is being conducted. SateUites which image portions of the earth's surface, or other space-based observation platforms use such mirrors. A high level of stability, structural and thermal, is required to obtain an acceptable image. Space-based applications may be exposed to extremes in temperature, which require an extraordinarily reliable and sound structure. Glass ceramics are suitable materials for such applications, since they exhibit excellent stabiHty during temperature fluctuations. One such glass ceramic is Zerodur®, which is an example of an especially preferred mirror blank material because it has exceUent dimensional stabiHty, owing to a CTE of less than 75 ppb/K from 0 - 50 °C. Other glass ceramics, based on Si0 2 - containing glasses, including Nexcera, a glass ceramic made by Nippon Steel, Tokyo, Japan, V02 or V20, a Hthium alumino siHcate glass ceramic produced in VR China Xi hu Factory, Shanghai, China, Clearceram, Astro-SitaU and Sitall, which are lithium alumino silicate glass ceramics produced by Lytkarino, Moscow, Russia are suitable for the practice of this invention. NormaUy, monolithic (i.e. soHd) mirrors are utilized to fabricate precision optics due to their ease of manufacture, dimensional stabiHty, and exceUent mechanical strength. A monoHthic mirror blank is fabricated from a single piece, having no joints, and such mirror blanks are usuaUy massive structures. For example, a standard, cylindrical Zerodur® mirror blank with a diameter of 1.5 m and a thickness of 0.25 m will have a mass of greater than 1,100 kilograms (i.e. greater than 2,400 pounds). Lifting and/ or automating such a massive weight often prevents the use of glass ceramic mirror blanks in flight or space- based appHcations. The present invention enables a series of components to be assembled, and can overcome the drawbacks associated with the large mass of monoHthic mirror blanks. Lightweight mirror blanks, which preferably consist of thin (preferably less than 5 cm) face and back plates, that are attached to a Hght- weighted core, as shown in Figure 1. These three components, i.e. face plate, back plate, and light-weighted core, are joined according to the present invention to form a stable, rigid, light-weighted mirror blank at low temperature. With reference to Figure 1, a novel Hght-weighted mirror blank according to the present invention is seen. The outer surfaces of the mirror blank 10 may be flat, curved, concave, convex, or any geometricaUy desired shape. The face and back plate are preferably between 0.5 cm and 5 cm in thickness, most preferably about 1-3 cm thick. Beneath, the face plate (from the perspective of figure 1) is a lattice of supporting elements 12 forming a light weighted core. Each of these elements is also preferably a glass-ceramic to yield a uniform coefficient of thermal expansion for the unit. The supporting elements are illustrated as aHgned in a crosshatched manner, but any suitable arrangement, which provides dimensional stabiHty, is acceptable. The supporting elements are preferably designed for sufficient stability without excessive weight. The elements may have voids driUed within (e.g. by water cutting or mechanical drilling) to further reduce the mass of material. Other shapes and styles of supporting elements may be designed by one of skiU in the art having regard for this disclosure. In an alternative embodiment, the light-weight core is formed from monoHthic Zerodur® by water-jet cutting, ultrasonic drilling, laser cutting, diamond saw drilling, etc. When such a light weight mirror blank is finished, the overall mass may be reduced by as much as 70% or more when compared to a monoHthic structure, yet retaining sufficient CTE and strength characteristics to be perfectly suitable for airborne or space borne appHcations where high tolerances are expected. Appropriate components (including a face plate, back plate, and Hght weighted core) should be selected to obtain the maximum benefits of the instant invention. For example, a plurality of components to be fabricated into a larger structure would be selected as follows. A plurality of components of glass ceramic with nearly identical CTE's are selected. By way of example, three slabs of Zerodur™ with nearly identical CTE (i.e., each within ±25 ppb/K) wiU be fabricated. In this example, a 30 cm mirror blank is to be fabricated. Two slabs wiU have nominal dimensions of 30 cm in diameter and 3 cm thick. These two slabs will form the face and back-plates of a light-weighted mirror blank according to the instant invention. The third slab wiU have a diameter and thickness of approximately, 30 cm and 4 cm, respectively. This third slab will be used to fabricate the light-weighted core. The two slabs intended for the face and back-plates are cut and/ or ground to an appropriate thickness, and then poHshed. The surfaces intended for joining are prepared with a surface figure of 1/3 λ («200 nm peak to vaUey). Although the face and back-plates may be flat, other geometric shapes are possible (i.e., they may be concave, convex, or of other suitable shape). A pluraHty of holes are driUed through the back-plate to reduce the overall weight of the mirror blank, and to provide an opening for each ceU within the Hght-weighted core. The slab intended for the light-weighted core is cut and ground to an appropriate thickness and then poHshed. Both surfaces of the core have a surface figure of 1/3 λ (∞200 nm peak to vaUey). Again, the core may be flat or of other geometric shape (i.e., either side could be concave, convex, or other suitable shape as appropriate to provide surfaces that will "mate" with the face and back plates during assembly). The core is then weight-reduced by removing excess material without compromising the structural integrity of the core. For example, it may be converted into a honeycomb-like shape by water-jet cutting, or any other method in the cutting art that can be used to transform a soHd piece of glass into a honeycomb-like structure (i.e., laser cutting, ultrasonic drilling, drUling and cutting with conventional equipment, etc.). The machined core wiU be referred to as the Hght-weighted core hereafter. If necessary, the surfaces of the light- weighted core are re-finished to remove any surface damage that results from the weight reducing step. After the component pieces are selected and prepared, the next step of the instant novel process preferably includes cleaning. Each component (face-plate, back-plate, Hght-weighted core) is, if necessary, cleaned simultaneously or independently, using the foUowing procedure: First, the components wiU be immersed in a cleaning solution comprised of 10 vol% Micro Solution and 90 vol% deionized H 2 O for approximately 30 minutes. This solution is preferably agitated by stirring, rocking, vibration or forced circulation. The cleaning solution is then removed and the component immersed in deionized H 2 0 for approximately 5 minutes. The component is then removed from the H 2 O and immersed in a KOH( aq ) solution (0.01 to 9.0 M) for approximately 5 minutes. Subsequently, the components are removed from the KOH(aq) solution and immersed in deionized H 2 0 for approximately 5 minutes. FinaUy, each component is rinsed with high purity (low residue) ethanol, then rinsed with high purity (low residue) methanol, and transported into a clean room environment. After transporting the components into the clean room, deionized N 2 gas will preferably be used to remove any residual methanol from the joining surfaces. OptionaUy, a CO 2 sno-gun is used to remove any dust or particulate debris from the joming surfaces. At this point, all joining surfaces are chemicaUy clean and free from particulate debris. The clean, dry components are then stored, such that their joining surfaces are not in contact with any source of particulate or chemical contamination. Once the component pieces are poHshed and cleaned to the requisite degree, the surfaces to be joined should be free of debris and contain a large concentration of sUanol (SI-OH) groups, as may be seen in figure 2. An exemplary sUicate "joining liquid" with the general oxide composition shown in Table I is prepared and is used for low temperature joining according to the present invention. The joining Hquid typicaUy contains sϋanol (Si(OH) ( aq )), alkali (Na + ( aq )) and other aqueous species (i.e., H2θ( aq ), H 3 0 + ( aq ), OH'( aq )). Although not wishing to be bound by the theory of joint formation, the notations under "comments" give a theoretical explanation for the functionality of species in the joining liquid. Table I: Compositional Space for the Joining Liquid Other suitable joining Hquids include Hthium siHcate Hquid, potassium siHcate Hquid, magnesium siHcate liquid, calcium siHcate liquid, barium siHcate Hquid, strontium sUicate Hquid, mixed alkali siHcate Hquid, mixed alkali/ alkaline earth sUicate liquid, mixed alkaline earth siHcate liquid, and sUicate Hquid, where "Hquid" refers to an aqueous solution. Joining is initiated by sandwiching the appropriate Hquid between two clean surfaces, as shown in Figure 3. Only a small volume ( preferably «0.5 μl/cm 2 ) of the joming liquid is required to form a strong joint. Larger or smaUer volumes may be used by one of skill in the art having regard for this disclosure. It is preferred that at a minimum there be at least 0.01 μl/cm 2 . In another embodiment of the present invention, ground or fritted glass- ceramic or glass, e.g., Zerodur® or siHca-containing glass or glass-ceramic, could be added to the joining liquid to form a stronger joint, fiU in voids at the joint interface, and promote joint dehydration. A joining liquid with the general composition shown in Table I is used to join the face and back plates to the Hght-weighted core. First, particulate debris is preferably removed from the joining Hquid using filtration and/ or centrifugation. The two joints required to fabricate a light-weighted mirror blank (face-plate to light-weighted core, and back-plate to Hght-weighted core) could be fabricated simultaneously, but preferably they are fabricated separately. Joining liquid is applied to one or both surfaces intended for joining (i.e., to the back of the faceplate and the mating side of the Hght-weighted core) by any of a number of coating techniques. For example, spin coating may be used, where an excess of joining liquid is to be applied to the surface, and then the majority removed by high-RPM spinning. Another appHcation technique is dip coating, where the surface is dipped into a vat of joining liquid of appropriate viscosity and then removed at an appropriate speed to ensure that an adequate volume (at least 0.01 μl/cm 2 ) of joining Hquid remained. Another suitable method is pipetting or auto-dispensing drops of joining Hquid at various points on the joining surface. Upon joining, these drops would spread and provide an adequate volume of joining Hquid. Yet another method contemplated by the instant invention includes joining the components whUe submerged in a vat of joining liquid, i.e. assembling the mirror blank whUe submerged. Another method cludes bringing the two components into contact and allowing the joining Hquid to be introduced from the side and be drawn between the two surfaces to be joined by capiUary action. CapUlary forces wiU "pull" the Hquid into the interfacial region and a joint wUl be formed. One skiUed in the art having regard for this disclosure may envision the use of any automated technique commonly used to dispense liquid in, e.g., the adhesives industry. In a preferred embodiment, reproducible volumes of joining Hquid are applied to the joining surfaces. In an especiaUy preferred embodiment, premature curing (hardening) of the Hquid prior to joining is avoided by performing the joining in a humid environment. The silicate liquid quickly dries under a dry atmosphere (<30% relative humidity) to form a residue, which results in an imperfect joint. For example, when making a joint at a low relative humidity <30% RH, the foUow g problems can occur: 1) Premature drying of the joining liquid resulting in a thick joint interface »1 micron. 2) Premature drying of the joining liquid resulting in joint turbidity. 3) Premature drying around the edges of a drop of joining Hquid that is applied to the joining surface resulting in a ring-shaped defect at the joint interface. 4) Debondmg after curing at room temperature. 5) Debonding after heat treatment at temperatures ranging from 30°C to 600°C. 6) Premature drying of the joining Hquid resulting in the inability to aHgn the pieces once in contact. 7) Near impossibility of evenly coating a compHcated light weighted structure prior to joining without encountering problems mentioned above. The problem is intensified as the volume of joining liquid is reduced (for instance from 0.5μL/cm 2 to 0.05μl/cm 2 ). In order to minimize these problems and to achieve defect reduced, strong joints, bonding should be conducted in a controUed humidity environment ranging from about 30% R.H. to about 100% R.H., preferably from about 60% R.H. to about 100% R.H., more preferably from about 75% R.H. to about 95% R.H. A particularly preferred condition is at about 80% relative humidity. A suitable time period range between solution appHcation and bonding contact of the surface, i.e., bonding, is from immediately after appHcation to about 10 minutes after application, preferably from immediately after appHcation to about 5 minutes after application, more preferably from immediately after appHcation to about 1 minute after application. It is particularly preferred to contact the surfaces as soon as possible after solution application. In a preferred embodiment, the faceplate is brought into contact with the Hght-weighted core using an alignment apparatus. The joining Hquid forms an interface between the two clean, poHshed (e.g., course or finely ground) surfaces. The joined component should be allowed to cure for at least 1 hour before attempting to fabricate the second joint. After allowing at least 1 hour for the first joint (face plate to Hght- weighted core) to cure, joining liquid will then be appHed to the back plate. The back plate is then brought into contact with opposite side of the light-weighted core using an alignment apparatus. The joining liquid then spreads and forms an interface between the two components. In an especially preferred embodiment, each hole in the back-plate is aHgned with each ceU (void) in the light- weighted core. Aligning the holes in the back-plate with the cells in the light-weighted core ensures that no air is trapped within the light-weighted mirror. Trapped air can be problematic, especiaUy when the mirror blank is used for an appHcation where appreciable temperature fluctuation can occur. Temperature fluctuations would change the ah pressure within an airtight compartment and could cause local variations in the surface figure of the front faceplate. Such local variations in surface figure could compromise the performance of the mirror. Although not wishing to be bound by the foUowing theoretical explanation, it is believed that the foUowing mechanism explains the development of such mechanically strong, low CTE joints by the low- temperature joining process. Once the liquid is sandwiched between the two surfaces, condensation reactions (Equation (1)) begin as silanol groups combine to form -Si-O-Si- Hnkages, while releasing (condensing) H 2 0. - Si - OH + OH- Si → -Si - O - Si - +H 2 0 (1) A rigid joint is formed when the -Si-O-Si- cross-linking spreads throughout the interfacial region and eventuaUy binds the two joining surfaces together, as shown in figure 3. The resulting joint is composed of a hydrated, siHcate solid. It is a sodium siHcate solid if a sodium siHcate liquid is used for the joining process. It is believed that the Si-O-Si- linkages are primarily responsible for joint strength. While the H 2 0 present in the interfacial region (i.e., that formed by condensation reactions and that originaUy present in the joining liquid) can evaporate from the joint interface, diffuse into the joining material, or form hydrogen bonds across the interface, it is beHeved that H 2 0 can also contribute to the overall joint strength. FinaUy, the Na + ions are expected to form chemical bonds between non-bridging oxygen (NBO) atoms within the joint interface. The result of -Si-O-Si- cross-linking, hydrogen bonding and Na + /NBO bonding is a rigid joint that typicaUy has a strength 4000 psi. The residual H 2 O that remains in the interfacial region after room temperature curing may contribute to the overall joint strength by providing hydrogen bonding. However, in an alternative embodiment of the present invention, the joint is dehydrated. If, for example, the end appHcation for the joint requires stabiHty at temperatures >100°C, removal of H2O wiU reduce the risk of failure. The fully joined, light-weighted mirror blank would be aUowed to cure at room temperature for at least 1 day, and preferably for 7 days before a dehydration should be attempted. Not all forms of dehydration will work in preparing joints according to the instant invention. For example, when Zerodur® - Zerodur® joints are prepared at room temperature and then subjected to microwave treatment, catastrophic failure generally occurs. Dehydration without catastrophic faUure can best be achieved by using a slow, controUed heat-treatment schedule according to the present invention. When small samples of glass-ceramic Zerodur® (30x20x10 mm, joining surface 10x10 mm) are fabricated according to the present invention, after 1-week room temperature cure, these joints are strong enough that they cannot be fractured by hand. When excessive force is applied, the resulting fracture does not necessarUy occur at the joint interface. When small Zerodur® - Zerodur® samples are fractured by impacting them on a hard surface, the fracture often results in pullout of material on either side of the joint interface. Zerodur® - Zerodur® joints formed at room temperature according to the instant invention show exceUent strength characteristics as evident from the flexural strength testing results shown in Figure 4. A room temperature cured Zerodur® - Zerodur® joint has a flexural strength, which can exceed 9,000 psi. The large flexural strengths (5,000 to 10,000 psi) achieved by joining and curing Zerodur® at room temperature are sufficient for space-based appHcations (where the allowable stress for Zerodur® is 750 psi). However, the strength and stability of such room-temperature-cured joints is deleteriously affected by temperature ramps (>10 K/h). Quickly heating room temperature cured Zerodur® - Zerodur® joints to temperatures >50°C (i.e., by subjecting the joint to excessive microwave radiation) will often cause catastrophic faUure. Although not wishing to be bound by this theory, it is believed that residual H 2 O at the joint interface is likely responsible for the strength degradation and proneness for faUure when Zerodur® - Zerodur® joints are quickly heated. When a room temperature cured, Zerodur® - Zerodur® joint is heated at >10 K/h to temperatures >50°C, the vapor pressure of H 2 O within the hydrated joint interface is increased. This increase in vapor pressure cannot necessarUy be accommodated by H2O diffusion into the bulk Zerodur®. As noted previously, Zerodur® is a glass ceramic, which contains «70 wt% of «50 nm Hthium alumino sUicate crystals in a matrix of silica-rich glass. Most diffusion models for glass-ceramics assume that the crystalline phase is impermeable to diffusing species, such as OH", H3θ + or H 2 O. Thus, the crystaUine nature of Zerodur® likely blocks H2O diffusion into the bulk, and it is believed that the only way for H2O to escape the hydrated joint interface is by surface diffusion to the edge of the sample, see Figure 6. Once the H 2 O reaches the edge of the joint, it can easily be removed by evaporation. When a Zerodur® - Zerodur® joint is rapidly heated, and the vapor pressure within flie joint interface is not offset by H 2 0 surface diffusion, interfacial damage or joint failure can occur. Interfacial damage is generally apparent in the form of small (1mm) bubbles that form at the joint interface. Such damage usually occurs when a room-temperature-cured, Zerodur® - Zerodur® joint is heated at >5 K/h in a furnace or oven. Sufficiently rapid heating (i.e., subjecting a room temperature cured Zerodur® - Zerodur® joint to microwave radiation, in a commercial microwave oven) often causes catastrophic faUure, as the joint simply "pops" apart. A novel slow and systematic heat-treating technique has been developed to dehydrate room-temperature-cured glass-ceramic and Zerodur® - Zerodur® joints. The heat-treatment schedule is shown in Table II. This heat-treatment schedule is suitable for joint dehydration where the mean free path for H 2 0 surface diffusion is preferably no greater than 12.5 mm. This exemplary treatment schedule is a preferred schedule; slower treatments are possible and may be preferable for different types of joints. Such treatment regimens may be easily developed by one skilled in the art having regard for this disclosure. Table II: Preferred Heat Treatment Schedule for Dehydratin 25x25 mm oints The strength of heat-treated Zerodur® - Zerodur® and other glass- ceramic joints may be sHghtly less than tiiose cured at room temperature (Figure 4), and this is likely due to the depletion of hydrogen bonding at the joint interface (as H 2 0 is removed by evaporation). However, the strength and dimensional stabiHty of such heat-treated joints are more than sufficient for use in Hght-weighted mirror blank appHcations and others requiring at least 750 psi strength. Figure 4 shows that the flexural strength of Zerodur® - Zerodur® joints is always at least five times greater than the aUowable stress for Zerodur®, regardless of heat-treatment temperature from 60 to 120°C. Furthermore, the dimensional stability does not seem to be affected by heat-treatments up to 120°C, since the CTE of Zerodur® - Zerodur® joints were not statisticaUy different from the average CTE of a monolithic Zerodur® slab (i.e., -26 ± 10 pb/K) as shown in Figure 5. Heat-treatment at temperatures above 120°C may further increase the strength of a Zerodur® - Zerodur® joint. The interfacial region that joins two Zerodur® sections together is essentiaUy a sol-gel derived material (i.e., the sodium silicate liquid (sol) was transformed to a rigid interfacial region (gel) by curing). Sol gel materials derived from sodium siHcate Hquid can be heat-treated at temperatures exceeding 600°C, to increase the density and strength. However, the primary goal of a low-temperature joining process is to avoid as much excessive heat treatment as is possible. In yet another preferred embodiment, such joined components may be overcoated with a polymeric coating to prevent the loss of dried joining Hquid after the joint has been cured. In many applications, the avoidance of particulate debris, such as flaked off dust, is highly desirable and the addition of a polymeric or other sealant coating is preferred. Although the foregoing discussion has been framed in terms of joining two or more glass ceramic structures, it is also possible to join a glass ceramic surface to other types of surfaces using the same procedures and considerations discussed above. Suitable other surfaces which can be joined to glass ceramic surfaces using the same siHcate joining liquid and considerations include surfaces of a glass, metallic, metaUic aUoy, crystalline, polymeric, etc. nature. TypicaUy, a surface can be joined to a glass ceramic surface in accordance with this invention as long as it has surface reactive groups which react with components of the joining Hquid to form bonds to both surfaces, e.g., which permit the formation of Si-bonds with the siHcon atoms in the joining Hquid, e.g., via -O-, -N-, -C-containing, -P- etc. bonds, e.g., surface OH, NH 2 , PO 4 , etc. groups, or carbonaceous groups containing, e.g., -O- or -P- atoms, etc. Suitable such surfaces include, for example, -SiO 2 (glass, non crystaUine) -quartz -Al 2 O 3 (aluminum oxide, crystalline) -multi component sUicate glass -BK-7 - ULE, a titanium sUicate glass produced by Corning, Inc, Corning New York -antimony siHcate glasses -low expansion metallic alloys (e.g., Invar) OptionaUy coated with a thin layer of SiO 2 -germanium glasses -teUurium glasses -borosiHcate glasses Thus, where a glass substrate is used, it is preferably a multi-component oxide glass, a non-oxide glass, or a mixed oxide glass. Preferred multi-component oxide glasses include sUicate, borate, germanate, teUuride, phosphate or aluminate glasses. Preferred non-oxide glasses are chalcogenide, fluoride, heavy metal fluoride (e.g., ZBLAN ® ) or sulfide (e.g., As 2 S 3 ) glass. A preferred mixed oxide/ fluoride glass is a fluorophosphate glass. Where a crystalline material is used it is preferably a single crystaUine material, e.g., a non-semiconducting material such as LiNb0 , a fluoride such as CaF 2 or LiF, a chloride such as NaCl or AgCl, an iodide such as KI, a bromide such as AgBr, or an oxide such as Sapphire (A1 2 0 3 ). Alternatively, the single crystaUine material may be a semiconducting material such as GaAs, InP, ZnS, ZnSe, ZnTe, Si or Ge. For joints to surfaces other than glass ceramics, the rate of heat treatment discussed above can be modified according to the nature of the non-glass ceramic surface. For example, for glasses such as siHca and other materials which have open networks through which water can escape from the joint interface or which are hygroscopic (e.g., phosphate later glasses) rates higher than the approximate value of 5°K/hr mentioned above may be appHcable, e.g., 6, 7, 8, 10°K/hr etc., depending on the substances involved. Routine experiments wiU readily determine suitable values. Moreover, the nature of the non-glass-ceramic material wiU also straightforwardly affect the temperature of heating. When glasses are joined, the maximum temperature should not exceed the lowest glass transaction temperature of the jointed materials. Analogously, the maximum temperature should not exceed any value which would adversely affect the properties of the joined materials. For example, when one material has a CTE lower than the others, routine care wiU be taken to ensure that temperatures are avoided which would cause one or more bonded surfaces to rupture or be stressed unacceptably. Although the foregoing discusses primarUy mirror surfaces, virtually any kind of device can benefit from this invention's surface joints, e.g., also etalons, vacuum chambers, low expansion structures in general, etc. Without further elaboration, it is beHeved that one skUled in the art can, using the preceding description, utilize the present invention to its fullest extent. The following preferred specific embodiments are, therefore, to be construed as merely Ulustrative, and not limitative of the remainder of the disclosure in any way whatsoever. In the foregoing and in the following examples, aU temperatures are set forth uncorrected in degrees Celsius; and, unless otherwise indicated, aU parts and percentages are by weight. The entire disclosures of aU applications, patents and pubHcations, cited above, and U.S. Serial No. 09/597,157 filed June 20, 2000, are hereby incorporated by reference. EXAMPLES Example 1 Zerodur® samples with approximate dimensions of 60x25x25 mm were used for aU joining experiments. One of the 25x25 mm faces on each sample was poHshed, with a surface figure of at least 1/3 λ (200 nm peak to vaUey, this surface will be referred to as the joining surface), while the other 25x25mm face was simply polished to a transparent finish. The joining surfaces were cleaned using various solutions. First, the samples were ultrasonically cleaned in a 10:90 volumetric ratio of Micro Cleaning Solution and deionized H 2 0. The samples were then rinsed with deionized H 2 0 before being ultrasonically cleaned with 3.0 M KOH( aq ) solution. After cleaning with KOH( aq ) solution, the samples were rinsed with deionized H 2 0, ethanol and methanol before being dried with deionized N 2 gas. Finally, a C0 2 sno-gun was used to remove particulate debris from the joining surfaces. The clean samples were placed within a clean, dust-free enclosure until joining was conducted. The Zerodur® samples were joined using a low temperature joining process. When making a joint by the low temperature joining process, sodium siHcate liquid is sandwiched between two clean, poHshed, joining surfaces. A mechanically strong joint is formed when ti e liquid cures and forms a rigid interface between the two joining surfaces. A sodium silicate Hquid containing «15 wt% SiO 2 and «6 wt% Na 2 O was used for aU Zerodur® - Zerodur® joining experiments conducted for strength evaluation. The joining liquid was prepared by diluting commercially available sodium sUicate liquid with deionized water. After dilution, the resulting Hquid was filtered with a 0.2 μm filter, before centrifugation was used to separate and remove any remaining particulate debris. A 3 μl drop of the centrifuged sodium sUicate joining liquid was appHed to the joining surface of a Zerodur® sample using a pipette. A second joining surface was then brought down upon the 3 μl drop to spread and sandwich the joining Hquid between the two Zerodur™ surfaces. All of the joining experiments were conducted in a clean, dust free enclosure. The joint assembly (two 60x25x25 mm samples joined with the sodium sUicate Hquid) was allowed to cure for at least 7 days at room temperature (15 to 30°C). Some joint assemblies were also heat-treated at temperatures ranging from 60 to 120°C. Flexural samples were machined from the room temperature cured and heat-treated joint assemblies, as shown in Figure 7. Care was taken during machining to ensure that the samples were not subjected to elevated temperatures (> 50°C) or corrosive liquids (i.e., acid-based pitch remover). The goal was to machine samples from the joint assembHes without deleteriously affecting the joint strength. The resulting flexural samples were nominally 3x4x45 mm, in accordance with the ASTM standard C1161-94 "Standard Test Method for Flexural Strength of Advanced Ceramics at Ambient Temperature." The 4x45 mm faces of the flexural specimens were ground with 20 μm A1 2 0 3 grinding media before flexural strength tests were conducted. Flexural strength testing was conducted in accordance with ASTM standard C1161-94. Flexural strength was measured for Zerodur® - Zerodur® joints that had been cured at room temperature, and those heat-treated at 60, 90, or 120°C for 20 h. The flexural strength of monoHthic Zerodur® was also measured for comparative purposes (note that the monoHthic Zerodur® flexural surfaces were also prepared with a 20 μm AI2O3 grinding media). The results from the flexural strength testing are shown in Figure 4. The average flexural strength of the Zerodur® - Zerodur® joints was greater than 5,000 psi, regardless of the heat-treatment temperature. However, the Zerodur® - Zerodur® joints always yielded a lower flexural strength than the monoHthic Zerodur® samples, which had an average flexural strength of >13,000 psi. A flexural strength of 5000 psi is more than six times greater than the aUowable working stress (750 psi), and more than three times greater than the ultimate handling stress (1,500 psi) for Zerodur®. Thus, Zerodur® - Zerodur® joints prepared by the low temperature joining process and heat treated at temperatures ranging from 60 to 120°C are expected to be suitably strong for use Hght-weighted Zerodur® mirror blanks. Example 2 The CTE of components joined according to the present invention is most preferably the same as that of monolithic glass ceramic materials. The minimization or eHmination of joint-induced CTE variation ensures dimensional stabUity when the mirror-blank is used for appHcations, such as remote sensing. Testing was conducted to determine whether a composite glass ceramic joint has the same CTE as monolithic glass ceramics. AU samples intended for CTE evaluation were obtained from the same slab of Zerodur® (Melt Number F- 9831). The intrinsic variation of CTE in the slab was determined by measuring the CTE at three positions. The three values of CTE were -33, -25 and -20 ppb/K (each CTE reported herein is an average value, measured from 0 to 50°C). Note that the typical measurement accuracy for the CTE in the temperature range of 0 to 50°C is ±10 ppb/K and the precision under repeatabiHty conditions is ±5 ppb/K. Therefore, the average CTE of the Zerodur® slab from 0 to 50 °C (Melt Number F-9831) was -26 ± 10 ppb/K. Samples with the nominal dimensions of 60x25x25 mm were used to prepare Zerodur® - Zerodur® joint assemblies for CTE evaluation. These samples were cleaned and joined using the same procedures described in the Mechanical Strength section (above). Two Zerodur® - Zerodur® joint assembHes were prepared for CTE evaluation and allowed to cure for at least 7 days at room temperature. A CTE rod (6 mm diameter) was core drUled from each of the two joint assemblies, as shown in Figure 8. The CTE of the first rod was measured before and after 20 hour heat- treatments at 60, 100 and 120°C, while the CTE of the second rod was measured before and after 20 hour heat-treatments at 60, 90 and 120°C. Figure 4 compares the CTE data collected from each of e joined CTE rods with the average CTE of the Zerodur™ slab (melt number F-9831). Note that all CTE data are within 10 ppb/K of the average CTE measured for the Zerodur® slab. Thus, the low temperature joining process does not affect CTE, and when the process according to the present invention is used to fabricate Hght-weighted Zerodur® mirror blanks, remarkably superior and stable composite structures are formed. Example 3 One general procedure that can be used to prevent the siHcate-containing joining Hquid from prematurely drying prior to bonding is as foUows. Strong bonds between Zerodur® pieces were made in a class 100 clean box with humidity control (+2% Relative Humidity) at ambient temperature. In one experiment, a poHshed face plate and poHshed back plate were jointed to a latticed 2-part polished rib structure assembled with slots as shown in Figure ID. In a second experiment, a water-jet cut Hght-weighted core was joined to a poHshed face plate and polished back plate. The bonding surface of the core was coarse ground. The face plate had four ventilation holes as Ulustrated in Figure IB to aUow dehydration of the joints. In a third experiment, 3mmx4mmx45mm paraUelpipeds were jomed on a 4mmx45mm fine ground side to a poHshed plate. The relative humidity was varied from 25-90% R.H. at ambient temperature. The time period between solution application and bonding was varied as weU from immediately after appHcation to 10 min. after appHcation. At RH values of 30% and higher, the joints were exceUent, e.g., at RH less than 30%, the joints had imperfections. The preceding examples can be repeated with simUar success by substituting the generically or specifically described reactants and/ or operating conditions of this invention for those used in the preceding examples. From the foregoing description, one skilled in the art can easily ascertain the essential characteristics of this invention and, without departing from the spirit and scope thereof, can make various changes and modifications of the invention to adapt it to various usages and conditions.

Claims: We claim: 1. A low-temperature process for the fabrication of lightweight composite glass ceramic structures, comprising: providing a pluraHty of glass ceramic components, said glass ceramic components each being polished to form at least one joining surface on each component, providing a siHcate-containing joining Hquid to at least one of the joining surfaces, bringing the joining surfaces of the plurality of glass components together to form a joint, allowing the joint to cure for a period of time of at least 20 hours at a temperature of at least 20 degrees C, whereby a cured joint is formed between said pluraHty of glass components, and dehydrating the cured joint graduaUy by raising the temperature slowly and maintaining an elevated temperature below the glass transition temperature of the glass ceramic for at least 20 hours. 2. A method as claimed in claim 1, wherein the step of dehydrating comprises graduaUy raising the temperature at a rate which allows dehydration of the joint without imparting damage to the joint from accelerated H 2 O evaporation. 3. A process as claimed in claim 1, wherein the glass ceramic components are Zerodur® components. 4. A process as claimed in claim 1, wherein the glass ceramic components include a low expansion material prepared by partiaUy ceramizing a Hthium alumino silicate glass. 5. A process as claimed in claim 1, wherein the glass ceramic components include a material selected from the group consisting of Nexcera, Clearceram, V02, AstrositaU and SitaU. 6. A process as claimed in claim 1, wherein the silicate containing liquid is a Hthium sUicate containing liquid or a sodium sUicate containing liquid. 7. A process as claimed in claim 1, wherein the siHcate containing Hquid is an alkaH siHcate, alkaline earth sUicate, mixed alkaH sUicate, mixed alkaline earth siHcate, or mixed alkaH/ alkaline earth silicate Hquid. 8. A process as claimed in claim 2, wherein the step of graduaUy raising the temperature comprises increasing the temperature at a rate less than or equal to 3 degrees K/hour. 9. A process as claimed in claim 8, wherein the temperature is periodicaUy stabilized and held. 10. A process as claimed in claim 9, wherein the temperature is stabiHzed at intervals of from 5 to 20 degrees C and held for at least 10 hours. 11. A process as claimed in claim 10, wherein the temperature is stabiHzed at intervals of about 10 degrees C and held for about 20 hours. 12. A process as claimed in claim 1, wherein the components include at least one component with a hollowed out light-weighted portion. 13. A process as claimed in claim 1, wherein the components comprise segments of a light-weighted core. 14. A process as claimed in claim 1, wherein the components include a mirror blank. 15. A process as claimed in claim 1, wherein the period of time is at least one hour. 16. A process as claimed in claim 1, wherein the period of time is at least one day. 17. A process as claimed in claim 1, wherein the period of time is at least one week. 18. A process as claimed in claim 1, wherein the step of providing the siHcate containing liquid comprises applying the sUicate containing Hquid in an amount of at least 0.01 microliter /cm 2 . 19. A process as claimed in claim 2, wherein the temperature is from 60 to 600 degrees C. 20. A process as claimed in claim 19, wherein the temperature is below 120 degrees C. 21. A glass ceramic composite, comprising: a pluraHty of glass ceramic components, said components being rigidly connected by a silicate-containing layer formed by curing a siHcate-containing Hquid between the glass ceramic components at a temperature of at least 20 degrees C for at least 20 hours. 22. A glass ceramic composite as claimed in claim 21, wherein the cured siHcate- containing layer is dehydrated at a temperature at or below 600 degrees C. 23. A glass ceramic composite as claimed in claim 22, wherein the cured siHcate- containing layer is dehydrated at a temperature at or below 120 degrees C. 24. A glass ceramic composite as claimed in claim 21, wherein the pluraHty of glass ceramic components comprise Zerodur components. 25. A glass ceramic composite as claimed in claim 21 wherein the pluraHty of glass ceramic components include a glass ceramic material prepared by partiaUy ceramizing a lithium alumino silicate glass. 26. A glass ceramic composite as claimed in claim 20, wherein the pluraHty of glass ceramic components include a material selected from the group consisting of Nexcera, Clearceram, V02, AstrositaU and SitaU. 27. A glass ceramic composite as claimed in claim 21, wherein at least one of the glass ceramic components contains a hollowed out space. 28. A glass ceramic composite as claimed in claim 21, wherein at least one of the components comprises a mirror blank. 29. A glass ceramic composite as claimed in claim 21, wherein the Hght weighted section is prepared by assembling separate segments of glass ceramic. 30. A glass ceramic composite as claimed in claim 16, wherein the rigid connection can withstand tensile stresses during usage of at least 750 psi. 31. A mirror blank suitable for use in space or flight appHcations comprising a plurality of glass ceramic components joined by a siHcate-containing Hquid and cured at a temperature of at least 20 degrees C. 32. A mirror blank as claimed in claim 31, wherein the mirror blank is formed from a face plate, a back plate, and at least one supporting element. 33. A mirror blank as claimed in claim 32, wherein there are a pluraHty of supporting elements. 34. A mirror blank as claimed in claim 33, wherein the pluraHty of supporting elements comprise crossed vertical walls, said vertical walls being provided with slots to form a lattice. 35. A mirror blank as claimed in claim 34, wherein each lattice opening forms a ceU, and the cell is provided with a ventilation hole or is open to the surrounding environment. 36. A composite glass ceramic structure suitable for use as a microHthography stage comprising a plurality of glass ceramic components joined by a siHcate- containing liquid and cured at a temperature of at least 20 degrees C. 37. A method of joining lightweight composite glass ceramic surfaces comprising applying to at least one of said surfaces a siHcate-containing solution and curing for an extended period at a slightly elevated temperature above room temperature. 38. A method as claimed in claim 37, wherein the temperature is from 30 to 50 degrees C, and the extended period is at least 20 hours. 39. A glass ceramic composite as claimed in claim 21, wherein said siHcate- containing layer comprises, in weight %, H 2 0 50-99.9 Si0 2 0.01-40 Li 2 0 0-20 Na 2 0 0-20 K 2 0 0-25 MgO 0-10 CaO 0-10 BaO 0-10 SrO 0-10. 40. A Hght weight glass-ceramic mirror blank, comprising: a face plate which is circular in shape, a back plate which corresponds in shape and size to the face plate, a plurality of support elements located between said face and back plates, said pluraHty of supporting elements forming a latticework said latticework and face plate and back plate defining a pluraHty of ceUs, said ceUs each being provided with a ventilation aperture or being open to the environment, said face plate, plurality of supporting elements, and back plate being joined by a siHcate-containing liquid in a plurality of joining steps to form a pluraHty of joints, and at each step, the joint cured at a temperature of at least 20 degrees C for a period of at least 20 hours. 41. A mirror blank as claimed in claim 1, wherein the joint is further dehydrated at a temperature of from 30 to 50 degrees C for at least 20 hours. 42. An optical or electrooptical device comprising a composite of claim 21. 43. A device of claim 42 which is an etalon. 44. A vacuum chamber comprising a composite of claim 21. 45. A composite of claim 21 which has a low coefficient of expansion. 46. A low-temperature process for the fabrication of a Hghtweight composite glass ceramic structure, comprising: providing at least two surfaces at least one of which is a glass ceramic, and the other of which is a glass-ceramic or another material having a surface group which reacts with a silicate joining liquid to form a stable bond, said surfaces each being poHshed to form joining surfaces on each, providing a silicate-containing joining Hquid to at least one of the joining surfaces, bringing the joining surfaces together to form a joint, aUowing tiie joint to cure for a period of time of at least 20 hours at a temperature of at least 20 degrees C, whereby a cured joint is formed between said surfaces, and dehydrating the cured joint graduaUy by raising the temperature slowly and maintainmg for at least 20 hours an elevated temperature below the lowest temperature at which one of tiie joined components is adversely affected. 47. A process of claim 46 wherein at least one of the surfaces is SiO 2 , quartz, Al 2 O 3 , multi component silicate glass, BK-7, ULE, antimony sUicate glass, a low expansion metallic alloy, optionally coated with a thin layer of SiO 2 , germanium glass, teUurium glass or borosilicate glass. 48. A process of claim 46 where at least one of the surfaces is a glass and said elevated temperature is below the lowest glass transition temperature of said joined surfaces. 49. A process as claimed in claim 46, wherein the glass ceramic component is a Zerodur® component. 50. A glass ceramic composite, comprising: at least two surfaces at least one of which is a glass ceramic and the other of which is a glass-ceramic or another material having a surface group which reacts with a silicate joining liquid to form a stable bond, said surfaces being rigidly connected by a sUicate-containing layer formed by curing a siHcate- containing Hquid between tih-e glass ceramic surface and said other surface at a temperature of at least 20 degrees C for at least 20 hours. 51. A glass ceramic composite as claimed in claim 21, wherein the glass ceramic surface comprises Zerodur®. 52. A glass ceramic composite of claim 21 wherein said other surface is SiO 2 , quartz, A1 2 0 3 , multi component silicate glass, BK-7, ULE, antimony sUicate glass, a low expansion metalHc alloy, optionally coated with a thin layer of SiO 2 , germanium glass, tellurium glass or borosUicate glass. 53. A process of claim 46 wherein said joining Hquid comprises ground or fritted siHca-containing glass-ceramic or glass.

Inventors: CONZONE SAMUEL DAVID, MARKER ALEXANDER J III, CONZONE, SAMUEL, DAVID, MARKER, ALEXANDER, J., III
Applicants: CONZONE SAMUEL DAVID, MARKER ALEXANDER J III, SCHOTT GLASS TECH INC, CONZONE, SAMUEL, DAVID, MARKER, ALEXANDER, J., III, SCHOTT GLASS TECHNOLOGIES, INC.
Application year: 2001
Main classification: C03C27
IPC codes: C03C27