Method for the growth of large single crystals

Abstract: A method is disclosed for producing large single crystals. According to the initial steps of this method, a plurality of single crystal wafers are crystallographically oriented to form a seed plate which is patterned. The patterned seed plate is selectively etched to expose the bare surface of the seed plate. The exposed, patterned bare surface of the seed plate is etched to form a plurality of nucleation structures. Each of the nucleation structures protrude outwardly from the underlying surface of the seed plate and provide ideal structures for the growth of large, single crystals. The resulting large, single crystals can be separated from the seed crystals by etching, physical or chemical means.

Description: FIELD OF THE INVENTION This invention relates to an alternative method to the method described in US-A-5,443,032 for the manufacture of large single crystals of diamond, which are difficult to manufacture in large dimensions. More particularly, the invention relates to a method for producing single crystal, electronic grade diamond wafers larger than single crystal diamond wafers that are currently available, i.e. areas greater than about 1 centimeter 2 (cm 2 ). BACKGROUND OF THE INVENTION Graphite is the most stable form of carbon under normal conditions, but at pressures of approximately 600,000 bar (atmospheres) and temperatures exceeding 1500°C, diamond is the thermodynamically stable phase. General Electric succeeded in growing synthetic diamond in the metastable region during the early 1950's by dissolving carbon in a molten transition metal at pressures in the range of about 40,000 to about 60,000 bar (atmospheres) and temperatures in the range of about 1200 to about 1600°C, i.e., high pressure, high temperature (HPHT) conditions, see H.T.Hall et al ., U.S. Patent No. 2,947,610. Diamond crystals nucleate and grow from molten carbon and metal solution, typically a nickel or iron solution. While most of the diamond crystals produced by HPHT conditions are under one millimeter (mm) for diamond grit applications, several corporations have been able to produce diamond crystals almost up to one cm. Due to the enormous difficulties with scaling up the pressure in large volumes at high temperature and difficulties with preserving the integrity of seals, only very moderate improvements in the size of diamond single crystals by the HPHT technique beyond one cm can be expected in the future. The ideal solution for the needs of the electronic industry would be hetero-epitaxial diamond on inexpensive substrates. Diamond via hetero-epitaxial chemical vapor deposition (CVD) has been reported on mm size cubic-boron nitride (C-BN) single crystal made by HPHT; see M.Yoshikawa et al ., Appl.Phys.Lett., Vol. 57, page 428 (1990). C-BN shows the most promise as a heteroepitaxial substrate for diamond due to similar structure, close lattice match and high surface energy. Unfortunately, only about 1 mm size crystal of cubic BN is available from HPHT techniques as of this date and the preparation of large single crystal cubic BN substrates from gas phase is very difficult and has not as yet been accomplished. An interesting technique has been disclosed which utilizes an array of 100 µm (0.1 mm) octahedron faceted HPHT diamond crystals fitted by spinning from a slurry into corresponding pyramidal etch pits onto a silicon wafer; see N.V.Geis et al ., Proceedings of the Second International Symposium on Diamond Materials, 179th Meeting of the Electrochemical Society in Washington, D.C., page 605, May 5, 1991. In this technique, commercially available (111)-faceted diamond seeds having diameters of 75 to 100 µm are deposited on (100)-oriented Si substrates which had been patterned and etched using standard photolithographic methods to form 90 µm square etch pits on 100 µm centers faceted on (111)-planes. Homoepitaxial diamond is grown on the diamond seeds to form a continuous diamond film composed of a plurality of approximately oriented small crystals. Self supporting continuous diamond films were obtained after etching away the silicon substrate. The diamond film contains low angle grain boundaries because diamond seeds are always misoriented by a few degrees. Textured growth on silicon or beta silicon carbide has much smaller diamond grain size on the order of a few microns across the single crystal grain, but the misorientation of individual grains is on the same order of magnitude in both cases. The disadvantages of the foregoing technique are that default holes occur in the resulting diamond film as a result of missing seed crystals in some of the etch pits and that a slight misorientation occurs among the individual single crystal grains. Therefore, this prior art technique does not produce a crystallographically perfect single crystal. The method of US-A-5,443,032 is directed to CVD diamond growth on a plurality of oriented single crystal diamond seed wafers which are patterned with a plurality of seed holes formed in such a way that newly grown single crystal diamond layer can be separated from a reusable diamond substrate. As a consequence of the orientation of two or more precisely oriented single crystal diamond patterned structures, a large diamond single crystal seed plate is generated by epitaxial fusion. R.A. Rudder et al ., has succeeded in depositing diamonds onto a photolithographically defined large electronic device area and has observed isotropic overgrowth advancing vertically and horizontally by about the same rate; see R.A. Rudder, J.B. Posthill, G.C. Hudson, D. Malta, R.E. Thomas, R.J. Markunas, T.P. Humphreys, R.J. Nemanich, Proceedings of the Second International Conference New Diamond Science and Technology, Washington, D.C., page 425, September 23-27, 1990. The Rudder et al . method includes the steps of depositing polycrystalline silicon onto a single diamond substrate; depositing a masking layer onto the Si layer; photolithographically opening holes to allow for the homoepitaxial diamond to nucleate; and depositing diamond onto the resulting substrate by CVD to form overgrowth extending over the Si pattern. The preceding reference does not teach separating the resultant deposited diamond layer from the substrate by any means such as mechanical, physical or cutting means. The reference also fails to teach growing a continuous monocrystalline (i.e., a single crystal) layer of material onto a substrate and then separating that material from the substrate. The quality of homoepitaxially grown diamond above the holes in the masking layer on the device was claimed to be superior to the quality of underlying diamond substrate; see J.B. Posthill, R.A. Rudder, G.C. Hudson, D.P. Malta, G.C. Fountain, R.E. Thomas, R.J. Markunas, T.P. Humphreys, R.J. Nemanich, Proceedings of the Second International Symposium on Diamond Materials, Proceedings Vol. 91-8 of the Electrochemical Society, May 5-10, 1991, page 274, Washington, D.C. The superior quality of a laterally propagated epitaxial layer is believed to be due to the so called "necking effect", which is frequently used in Bridgman or Czochralski crystal growth. Necking down the growing crystal limits the propagation of dislocation from the seed crystal only to the straight direction of growth, but not in lateral directions. In the references mentioned above, R.A. Rudder and J.B. Posthill have demonstrated that the same effect of lateral overgrowth which is being used successfully in silicon and gallium arsenide microelectronics for the fabrication of three dimensional integrated circuits can be used to fabricate three dimensional integrated circuits in diamond microelectronics technology. The reference does not teach using this technology to grow large monocrystalline diamond plates. Anthony et al ., U.S. Patent No. 5,264,071, teach a chemical vapor deposition (CVD) method for making a monolithic polycrystalline ( i.e., multiple crystals) diamond sheet in which a diamond is deposited onto a non-diamond substrate which is smooth and free of surface irregularities to reduce physical bonding between such irregularities to the deposited polycrystalline CVD diamond. The polycrystalline diamond sheet is separated from the substrate by a cooling step or by dissolving the entire substrate after the deposition to facilitate the release of the diamond sheet from the polished, metallic substrate. GB-A-1 601 206 discloses a method of enhancing epitaxy or preferred orientation comprising forming at predetermined locations a plurality of artificial defects at the surface of a substrate and thereafter depositing a film on said surface. The electronic industry is using large semiconductor single crystal wafers ranging in size from 5 cm to 20 cm in diameter. Wafers smaller than 5 cm in diameter currently cannot be economically produced. Therefore, for the electronic industry desires free-standing single crystal diamond wafers which are larger than 5 cm in diameter, so that the electronic industry can take advantage of the outstanding electronic properties of diamond. In order to take full advantage of diamond's outstanding electronic properties, diamond large free-standing single crystal wafers must be true single crystals which do not possess large angle grain boundaries and should be at least comparable in quality to the best natural diamond single crystal. Polycrystalline diamond films which deviate from the ideal orientation of single crystal by as little as 0.2 degree will display inferior electronic properties by the virtue of the presence of large angle grain boundaries. Large angle grain boundaries cause impurities to segregate on the interface between the grains and display an undesirable concentration of structural defects and electrical defects. These textured quasi-epitaxial diamond films or crystalline diamond structures demonstrate inferior electrical properties. SUMMARY OF THE INVENTION In contrast to the techniques disclosed in the prior art, the present invention is capable of generating large single crystals having high monocrystalline perfection which can be used in electronic, optical, mechanical and other applications. This result is accomplished by producing a highly perfect free-standing single crystal diamond wafer which is comprised primarily of low angle grain boundaries. According to the present invention a method of growing single crystal diamond by chemical vapor deposition, comprising depositing a masking layer on to a surface of a seed plate comprising a plurality of crystallographically oriented single crystal wafers, selectively etching the masking layer to form therein a geometric pattern of exposed seed plate surface, placing the seed plate into a chemical vapor deposition reactor, growing a single crystal on exposed surface of the seed plate and laterally therefrom to form a continuous layer of monocrystalline material coterminous with the plate and separating and recovering the resulting single crystal from the seed plate is characterised in that after the formation of said geometric pattern said exposed seed plate surface is etched to form a plurality of nucleation structures, consisting of the seed plate material and the remaining portion of said masking layer, which protrude upwardly from said seed plate, each of said structures having side walls and a top surface having a surface area in the range of 0.2 to 60 µm 2 ; the remainder of said masking layer is removed from said structures; coating material is deposited on said seed plate, submerging said structures; and a layer of the coating is removed to expose the top surface of said structures, whereafter the plate is placed in the chemical vapor deposition reactor and crystal growth proceeds from said exposed top surface of said structures to form a single crystal diamond having an area greater than the area of each of the individual crystal wafers. The coating material may comprise soft carbon, carbon soot, graphite, diamond-like carbon, hydrogenated diamond-like carbon, submicron-sized metal powder, and/or aliphatic epoxy polymer. The single crystal diamond which is formed is typically from 1µm to 1 cm thick, advantageously 50-1000µm thick. The side walls are preferably substantially normal to the surface of the seed plate and the etching to form nucleation structures is conveniently effected by oxygen anisotropic etching. In a representative embodiment of the invention, 6.25 x 10 6 nucleation structures are formed per cm 2 of said seed plate surface. Each of the nucleation structures comprises walls and a top surface having an area in the range of about 5 to about 90% of the surface area of the original seed plate. More particularly, each nucleation structure comprises a protrusion mesa having side walls and a geometrically patterned top surface having a surface area in the range of about 0.2 to about 60 µm 2 . The geometric pattern can possess any shape including a triangle or circle, and the preferred pattern is a square. In the method of the invention a continuous layer of monocrystalline diamond is formed over a period of time to achieve a thickness in the range of about 1 µm to about 1 cm. A thickness in the range of about 50 µm to about 1,000 µm is preferred. In one embodiment of the method of the present invention, the growth of the monocrystalline material initially proceeds with approximately the same growth rate on the top surfaces and the side walls of the mesas as well as the underlying surface of the seed plate. In this embodiment, a series of interconnecting channels are created within the monocrystalline material, i.e., between the growth of monocrystalline material on the side walls of the mesas and the underlying surface of the seed plate and below the monocrystalline material overlying the spaces between the top surfaces of the mesas. When the gaps between the top surfaces of the mesas have been closed, a continuous layer of the monocrystalline material continues to grow on such top surfaces and on the closed gaps between the top surfaces. There are a number of methods to modify the seed plate so that most of the subsequent single crystal growth is deposited on the top surfaces of the mesas and on the closed gaps. Such methods should prevent or slow down the single crystal growth anywhere else on the side walls of the mesas and prevent or slow down single crystal growth on the substrate underlying these open spaces. During the initial steps of another embodiment of the present invention, the etching step forms mesas to insure that the side walls are substantially straight, i.e., the side walls are substantially normal to the horizontal plane of the seed plate. This structure is obtained by impinging an oxidizing beam substantially normal to the horizontal plane of the substrate. The top surfaces of the resulting seed plate recovered from this embodiment are deposited with a relatively thick layer of a coating material having a thickness ranging from about 5 µm to about 30 µm. This can be accomplished by depositing a suitable coating material onto the entire surface of the substrate. Suitable coating materials include soft carbon, carbon soot, graphite, diamond-like carbon, hydrogenated diamond-like carbon, graphite, submicron-sized metal powder, aliphatic epoxy polymers, and mixtures thereof. Initially, the coating material covers the entire surfaces including the side walls and the top surfaces of the nucleation structures and the underlying substrate. The resulting masked seed plate is planerized by polishing so that only the top surfaces of the mesas are uncovered, but the spaces between the mesas are protected by the coating meterial. The top surfaces of bare mesas function as single crystal nuclei for the initiation of crystalline growth. After the termination of the crystalline growth cycle, the newly grown single crystal is separated from the diamond substrate by any etching, mechanical or chemical means. In a variation of the above embodiment of the present invention, the top surfaces of the seed plate are deposited with a relatively thick layer of a graphite material. This can be done by the steps of spinning an emulsion of graphite or other easily combustible coating material on the top of the mesas and drying the emulsion. Alternatively, the step of spinning can be replaced by the step of dipping the mesas in the emulsion. These steps of spinning or dipping and drying are repeated several times until a build up of graphite exists to completely cover the side walls and the top surfaces of the mesas and the underlying substrate. In this embodiment, the resulting completely masked seed plate is also planerized by polishing to uncover the top surface of the mesas and to leave the rest of the seed plate protected by porous, dried graphite. The resulting masked seed plate, with only the top surfaces of the mesas free of graphite, is placed on a suitable wafer holder in a CVD reactor. In this embodiment, the resultant fully grown epitaxial crystal is separated from the seed plate by etching or burning out the remainder of the graphite material and etching or burning through the cross-sectional areas of the mesas of the seed plate between the underlying surface and the top surface of mesas. Specifically, the composite is subjected to an oxidizing atmosphere at temperatures in the range of about 650° to about 1000°C for a sufficient period of time to etch through about cross-sectional areas of the mesas connecting the newly grown single crystal with the underlying substrate until separation occurs. The single crystal recovered from this process has an area that is greater than each of the plurality of crystal wafers that comprise the seed plate. During the initial steps of still another embodiment of the present invention, the etching step forms each of the plurality of mesas in the shape of an inverted pyramid with the base of pyramid being the top surface of the mesa and the apex being attached to the underlying substrate. This is done, for example, by impinging an oxidizing beam at an angle of substantially less than 90° from the normal plane of the single crystal diamond substrate while the substrate is being rotated. Preferably the oxidizing beam is directed at an angle in the range of about 15° to about 55° from the normal, and still more preferably at an angle in the range of about 17° to about 45°. BRIEF DESCRIPTION OF THE DRAWINGS Further features and advantages of the method disclosed herein will become apparent from the following and more particular description of the preferred embodiment of the invention as illustrated in the accompanying drawings (not to scale), in which: FIGURES 1-7 (the proportions in these figures are distorted to more clearly illustrate critical features) are schematic illustrations of the step-by-step fabrication of a diamond single crystal in accordance with the present invention. DETAILED DESCRIPTION OF THE INVENTION During the embodiment of the present invention which is illustrated in FIGURES 1-7 and set forth in detail in Example 1, a coating material layer is used comprising graphite, soft carbon, soot, diamond-like carbon, pyrolyzed polymers and similar carbonaceous materials which are easily combusted. The epitaxially grown crystal layer is separated from the seed plate by etching the coating material at temperatures in the range of about 250° to about 600°C in the presence of an oxygen-containing atmosphere and raising the temperature in the range of about 600° to about 900°C to etch away the diamond mesas. The commercially important feature of the present invention is that after the large, epitaxially grown crystal layer is separated from the seed plate, the resulting separated large crystal can be used to produce additional single crystals. Once an inventory of seed plates of varying lengths and widths ranging in area from about 2 to about 40 cm 2 has been manufactured, the seed plates are patterned masked and placed directly into the crystal growing reactor for replication of single crystals of substantially the same area. The method of the present invention produces large crystals using small crystal starting materials, i.e., the seed plate, such as natural and HPHT synthetic diamond crystals which are available in sizes up to about 1 cm 2 . Diamond growth for the purpose of this invention can be accomplished by any technique capable of growing diamond epitaxial layers, which is not detrimental to the masking layer. The exact crystal growing techniques that are used to grow the large crystals by the present method are not critical. The following list of techniques is illustrative, but not exhaustive: hot filament CVD (HFCVD) , microwave-assisted CVD, radio frequency plasma CVD (RFCVD), DC plasma assisted CVD, electron assisted CVD, Electron Cyclotron Resonance (ECR) plasma CVD, DC or AC arc plasma jet, and combustion flame diamond growth deposition. The following references provide an illustration of the state of the art of such techniques: U.S. Patent Numbers 4,767,608; 4,740,263; 4,734,339 and 4,707,384. One of the most frequently used chemical compounds for diamond growth is methane (0.1-7% vol.) with hydrogen gas making up the balance. Methane can be replaced with a variety of other compounds containing carbon, hydrogen, halogen, and sometimes oxygen. The following hydrocarbons have been successfully used: methane, ethane, propane, acetylene, ethene and benzene. The use of organic compounds such as methyl alcohol, ethyl alcohol, acetone, acetic acid typically results in faster diamond growth rates. Halogens or halocarbons based mixtures with hydrocarbons or alcohols and small oxygen addition allow growth of diamond crystal at lower temperatures. A carbon monoxide mixture (e.g. 15% by volume) with hydrogen is also known to result in good quality diamond growth. Oxygen and water are sometimes added to carbon-containing mixtures in order to modify the character of crystal growth. Inert gases are also sometimes added to reaction mixture. The purity of gases is critical for electronic applications in respect to species that become incorporated in the diamond crystal and are either electrically active or result in formation of inclusions. An example of an undesirable impurity is nitrogen. On the other hand, electrically active impurities are sometimes deliberately added in order to render the diamond crystal electrically conductive. Examples of such desirable impurities include diborane or some other boron compounds, which make diamond a p-type conductor. Suitable temperatures for conducting the growth step can be chosen from 350° to 1250°C. The preferred temperature range for HFCVD with 1% methane and 99% hydrogen is 600°-1050°C at 4000 Pa (30 Torr) pressure in the reactor. The gas mixture pressure depends on the particular technique used. Typical pressure for the HFCVD technique ranges between 2666-10664 Pa (20-80 Torr). The range of gas pressure is from low pressures, i.e. 66.65Pa (0.5 Torr) which is sometimes used in RFCVD, to 1 bar (atm), which is sometimes used in the DC arc jet technique. The flow rate of the gas mixture depends on the specific crystal growing technique used and the size of the crystal growing reactor. Gas flow rates for a 5 cm diameter HFCVD reactor range from 1 cm 3 /min. to 100 cm 3 /min., preferably in the range 5 cm 3 /min. to 15 cm 3 /min. The masking layer can be deposited onto the diamond seed by a number of techniques routinely used in the semiconductor industry such as evaporation, sputtering, ion beam deposition, CVD and the like. Patterning of the masking layer can be done by standard photolithographical techniques routinely used for manufacturing devices in semiconductor industry. A photolithographical mask is typically designed which allows for printing a design on the photoresist, spun off on a masking layer on the top of diamond seed. The design consists of circles or squares or other geometrical figures with dimensions from 0.1µm - 10µm separated by distance of 0.5-20.0µm on a rectangular, hexagonal or other grid pattern. The thickness of the masking layer typically ranges from 0.01µm to 5µm with the preferred range from 0.1µm - 2µm. In the preferred embodiment of the present invention, HFCVD and microwave-assisted CVD reactors have been used to manufacture large single diamond crystals. A general description of the type of HFCVD reactors and the process conditions suitable for depositing such diamond crystals via HFCVD are set forth in U.S. Patent No. 5,126,206, issued June 30, 1992. A general description of the type of microwave-assisted CVD reactors and the process conditions suitable for depositing such diamond crystals via microwave-assisted CVD are set forth in A. R. Badzian. T. Badzian, R. Roy, R. Messier, K. E. Spear, "Crystallization of Diamond Crystals and Films By Microwave-Assisted CVD [II] ", Mat. Res. Bulletin, Vol. 23, pages 531-548 (1988). The following example is provided to further illustrate Applicants' invention. Example 1 which follows describes an embodiment of the method of the invention which is illustrated in FIGURES 1-7. EXAMPLE 1 MANUFACTURE OF FREE STANDING SINGLE CRYSTAL DIAMOND USING A NUCLEATION STRUCTURE HAVING CYLINDRICAL MEAS NUCLEI Natural II.A type diamond single crystal square substrate of (100) orientation and 8 mm x 8 mm x 0.25 mm dimensions was used as seed plate 70 for crystal growth. The diamond seed plate was cleaned with organic solvents by rinsing 2 min. in trichloroethane, 2 min. in acetone, 2 min. in ethyl alcohol and 5 min. in deionized water, and blown dry with nitrogen gas. Next, the wafer was placed in ion beam sputtering machine in order to deposit on its polished surface, 0.5µm of silicon dioxide. After pulling a vacuum of 666.5x10 -6 Pa (5 x 10 -6 Torr), the diamond substrate was precleaned with an argon ion beam generated from an 11 cm diameter Kaufman source at 500 eV and 137 mA for 1 min. Following the precleaning step, 0.5 µm of silicon dioxide was deposited from a silicon dioxide source bombarded with argon ion beam generated from a 5 cm diameter Kaufman source at 1000 eV and 100 mA at 1.3x10 -2 Pa (1 x 10 -4 Torr). The deposition rate of silicor dioxide was 10 nm (100 Å)/min. This 0.5 µm silicon dioxide layer was used as masking layer 72 in which 2 µm diameter mesas on 4 µm centers on an rectangular grid were formed by the following photolithographical procedure. After spinning positive photoresist at 5,000 rpm for 20 sec. and 90°C bake, the photoresist layer 74 on the top of the substrate was exposed in the mask aligner with the appropriate mask for 20 sec. and developed for 40 sec. in a developer. This step formed the mesas in photoresist. Unprotected area of silicon dioxide masking layer were etched away by buffered hydrofluoric acid until the diamond surface was reached (FIG.1). Photoresist stripper a 70°C for 10 min. was used to remove the remainder of the photoresist 74, followed by a three times repeated rinse procedure of acetone, methanol and deionized water. The resulting patterned diamond substrate was dried in oven at 120°C for 15 min. In the next step, a selected depth of the unprotected diamond surface is removed by an oxygen anisotropic etching in a parallel plate reactive ion etching machine (RIE). After 30 min., 10 µm of diamond were removed from the surface by an anisotropic oxygen etching. A rectangular array of 10 µm tall mesas 76 were established by this procedure on the surface of diamond single crystal substrate. Protective cap 72 of silicon oxide on the tops of the mesas was etched away by buffered hydrofluoric acid. Following the removal of silicon oxide from the tops of the mesas, a protective masking layer is established in such way as to prevent diamond growth on the surface of the diamond substrate and on the diamond mesas' walls. This can be done by the number of ways and the following example demonstrate just one possible procedure. In this procedure, several applications of graphite emulsion were build up on the surface of the structure so that diamond mesas were completely covered by the graphite emulsion 80 (FIG.3). After drying the structure in the oven at 120°C for 30 min., the structure was planerized by polishing so that only the tops 82 of the diamond mesas were uncovered, but the rest of the nucleation structures were protected by porous, dried graphite 84 (FIG. 4). The tops of bare diamond mesas function as diamond single crystal nuclei for the initiation of diamond growth. This artificial diamond nucleation structure was then placed on wafer holder in an HFCVD reactor for diamond epitaxial growth. The details of the HFCVD reactor used in this example is described in U.S. Patent No. 5,160,544, issued November 3, 1992, the details of which are incorporated by reference herein. After the distance between a carburized hot filament and the artificial nucleation structure had been adjusted to about 10 mm, the HFCVD reactor was refilled with helium and evacuated. A mixture of 1% methane and 99% of hydrogen (99.999% purity) was then admitted into the reactor at a flow rate of 10 sccm/min. and the pressure was adjusted to 4000 Pa (30 Torr). The temperature of the patterned diamond substrate was raised to 900°C at a rate of 100°C/min. The temperature of hot filament was maintained at about 2300°C throughout the diamond epitaxial growth. Initial diamond nuclei 94 began to grow above the mesas as shown in FIG. 5. Epitaxial growth of diamond was carried out for 500 hours at a diamond growth rate of 0.5µm/hour. At the termination of growth cycle, helium gas was admitted to the HFCVD reactor at 4000 Pa (30 Torr) and a flow rate of 10 sccm/min. The resulting new diamond single crystal 94 on the artificial diamond nucleation structure was cooled at a rate of 100°C/min. to room temperature. The increase in the thickness of the new composite was measured to be 250 µm, which was due to the newly grown diamond single crystal above the artificial nucleation structure (FIG. 6). After the termination of the crystal growth cycle, the undesirable diamond growth on the sides of artificial nucleation structure was cut away with laser and the newly grown, 250 µm thick diamond single crystal 94 was then separated from the diamond substrate 70 by etching in an oxidizing atmosphere. Specifically, the composite was subjected to air at 750°C for a sufficient period of time to etch the remainder of the graphite masking layer and etch through the 2 µm diamond mesas connecting the newly grown single crystal diamond with the original diamond substrate until separation occurred (FIG. 7). Various other embodiments and aspects of our invention will occur to those skilled in the art without departing from the scope of the invention. Having thus described the present invention, what is now deemed appropriate for Letter Patent is set forth in the following appended claims.

Claims: A method of growing single crystal diamond by chemical vapor deposition comprising: depositing a masking layer on to a surface of a seed plate comprising a plurality of crystallographically oriented single crystal wafers; selectively etching the masking layer to form therein a geometric pattern of exposed seed plate surface; placing the seed plate into a chemical vapor deposition reactor; growing a single crystal on exposed surface of the seed plate and laterally therefrom to form a continuous layer of monocrystalline material coterminous with the plate; and separating and recovering the resulting single crystal from the seed plate characterised in that after the formation of said geometric pattern said exposed seed plate surface is etched to form a plurality of nucleation structures, consisting of the seed plate material and the remaining portion of said masking layer, which protrude upwardly from said seed plate, each of said structures having side walls and a top surface having a surface area in the range of 0.2 to 60 µm 2 ; the remainder of said masking layer is removed from said structures; coating material is deposited on said seed plate, submerging said structures; and a layer of the coating is removed to expose the top surface of said structures, whereafter the plate is placed in the chemical vapor deposition reactor and crystal growth proceeds from said exposed top surface of said structures to form a single crystal diamond having an area greater than the area of each of the individual crystal wafers. A method according to claim 1 wherein said coating material comprises soft carbon, carbon soot, graphite, diamond-like carbon, hydrogenated diamond-like carbon, submicron-sized metal powder, and/or aliphatic epoxy polymer. A method according to claim 1 or claim 2 wherein the single crystal diamond which is formed is from 1 µm to 1 cm thick. A method according to claim 3 wherein said crystal is 50-1000µm thick. A method according to any preceding claim wherein said side walls are substantially normal to the surface of the seed plate and said etching to form nucleation structures is effected by oxygen anisotropic etching. A method according to any preceding claim wherein 6.25 x 10 6 nucleation structures are formed per cm 2 of said seed plate surface.

Inventors: HOOVER DAVID SAMUEL, VICHR MIROSLAV, HOOVER, DAVID SAMUEL, VICHR, MIROSLAV
Applicants: AIR PROD & CHEM, AIR PRODUCTS AND CHEMICALS, INC.
Application year: 1996
Main classification: C30B25
IPC codes: C30B25, H01L21, C30B33