WO2003094218A2

WO2003094218A2 - Method of growing monocrystalline oxide having a semiconductor device thereon

Info

Publication number: WO2003094218A2
Application number: PCT/US2003/013008
Authority: WO
Inventors: Hao Li; Ravindranath Droopad; Dan S. Marshall; Yi Wei; Xiao M. Hu; Yong Liang
Original assignee: Freescale Semiconductor, Inc.
Priority date: 2002-05-03
Filing date: 2003-04-24
Publication date: 2003-11-13
Also published as: WO2003094218A3; CN100359648C; AU2003231131A1; AU2003231131A8; US6916717B2; KR20040108771A; CN1650407A; JP2005524977A; US20030207589A1

Abstract

High quality monocrystalline metal oxide layers (74) are grown on a monocrystalline substrate (72) such as a silicon wafer. The monocrystalline metal oxide is grown on the silicon substrate at a temperature low enough to prevent deleterious and simultaneous oxidation of the silicon substrate. After a layer of 1-3 monolayers of the monocrystalline oxide is grown, the growth is stopped and the crystal quality of that layer is improved by a higher temperature anneal. Following the anneal, the thickness of the layer can be increased by restarting the low temperature growth. An amorphous silicon oxide layer (78) can be grown at the interface between the monocrystalline metal oxide layer and the silicon substrate after the thickness of the monocrystalline oxide reaches a few monolayers.

Description

MONOCRYSTALLINE OXIDE HAVING A SEMICONDUCTOR DEVICE

THEREON

Field of the Invention This invention relates generally to semiconductor structures and devices and to a method for their fabrication, and more specifically to semiconductor structures and devices and to the fabrication and use of semiconductor structures, devices, and integrated circuits that include a monocrystalline material layer comprised of semiconductor material, compound semiconductor material, and/or other types of material such as metals and non-metals, and still more specifically to a method for growing a monocrystalline oxide layer on a monocrystalline substrate and to a method for fabricating semiconductor structures and devices that include such an oxide layer.

Background of the Invention

Semiconductor devices often include multiple layers of conductive, insulating, and semiconductive layers. Often the desirable properties of such layers improve with the crystallinity of the layer. For example, the electron mobility and band gap of semiconductive layers improves as the crystallinity of the layer increases. Similarly, the free electron concentration of conductive layers and the electron charge displacement and electron energy recoverability of insulative or dielectric films improves as the crystallinity of these layers increases.

For many years, attempts have been made to grow various monolithic thin films on a foreign substrate such as silicon (Si). To achieve optimal characteristics of the various monolithic layers, however, a monocrystalline film of high crystalline quality is desired. Attempts have been made, for example, to grow various monocrystalline layers on a substrate such as germanium, silicon, and various insulators. These attempts have generally been unsuccessful because lattice mismatches between the host crystal and the grown crystal have caused the resulting layer of monocrystalline material to be of low crystalline quality.

If a large area thin film of high quality monocrystalline material was available at low cost, a variety of semiconductor devices could advantageously be If a large area thin film of high quality monocrystalline material was available at low cost, a variety of semiconductor devices could advantageously be fabricated in or using that film at a low cost compared to the cost of fabricating such devices beginning with a bulk wafer of the monocrystalline material or fabricating such devices in an epitaxial film of such material on a bulk wafer of the same material. In addition, if a thin film of high quality monocrystalline material could be realized beginning with a bulk wafer such as a silicon wafer, an integrated device structure could be achieved that took advantage of the best properties of both the silicon and the high quality monocrystalline material. Accordingly, a need exists for a semiconductor structure that provides a high quality monocrystalline film or layer over another monocrystalline material and for a process for making such a structure. Further, a need exists for a method of fabricating a heterogeneous semiconductor structure that provides a high quality monocrystalline film or layer over another monocrystalline material. In other words, there is a need for providing the formation of a monocrystalline substrate that is compliant with a high quality monocrystalline material layer so that true two dimensional growth can be achieved for the formation of quality semiconductor structures, devices and integrated circuits having grown monocrystalline film having the same crystal orientation as an underlying substrate and especially for the formation of a high quality heteroepitaxial monocrystalline oxide layer overlying a monocrystalline substrate.

Further, there is a need for a method for fabricating semiconductor structures having a grown monocrystalline film, either semiconductor, compound semiconductor, insulative, or metallic, overlying a monocrystalline oxide film that, in turn, overlies a monocrystalline substrate. To achieve these needs, there is a further need for a method for growing a monocrystalline oxide of high crystalline quality on a monocrystalline semiconductor substrate.

Brief Description of the Drawings The present invention is illustrated by way of example and not limitation in the accompanying figures, in which like references indicate similar elements, and in which: FIGS. 1-4 illustrate schematically, in cross section, device structures in accordance with various embodiments of the invention;

FIG. 5 illustrates graphically the relationship between maximum attainable film thickness and lattice mismatch between a host crystal and a grown crystalline overlayer;

FIG. 6 illustrates a high resolution Transmission Electron Micrograph of a structure including a monocrystalline accommodating buffer layer;

FIG. 7 illustrates an x-ray diffraction spectrum of a structure including a monocrystalline accommodating buffer layer; FIG. 8 illustrates a high resolution Transmission Electron Micrograph of a structure including an amorphous oxide layer;

FIG. 9 illustrates an x-ray diffraction spectrum of a structure including an amorphous oxide layer;

FIGS. 10-13 illustrate schematically, in cross-section, the formation of a device structure in accordance with another embodiment of the invention; and

FIG. 14 illustrates schematically, in cross-section, the formation of a device structure in accordance with still another embodiment of the invention.

Skilled artisans will appreciate that elements in the figures are illustrated for simplicity and clarity and have not necessarily been drawn to scale. For example, the dimensions of some of the elements in the figures may be exaggerated relative to other elements to help to improve understanding of embodiments of the present invention.

Detailed Description of the Drawings

FIG. 1 illustrates schematically, in cross section, a portion of a semiconductor structure 20 in accordance with an embodiment of the invention. Semiconductor structure 20 includes a monocrystalline substrate 22, accommodating buffer layer 24 comprising a monocrystalline material, and a monocrystalline material layer 26. In this context, the term "monocrystalline" shall have the meaning commonly used within the semiconductor industry. The term shall refer to materials that are a single crystal or that are substantially a single crystal and shall include those materials having a relatively small number of defects such as dislocations and the like as are commonly found in substrates of silicon or germanium or mixtures of silicon and germanium and epitaxial layers of such materials commonly found in the semiconductor industry. In accordance with one embodiment of the invention, structure 20 also includes an amorphous intermediate layer 28 positioned between substrate 22 and accommodating buffer layer 24. Structure 20 may also include a template layer 30 between the accommodating buffer layer and monocrystalline material layer 26. As will be explained more fully below, the template layer helps to initiate the growth of the monocrystalline material layer on the accommodating buffer layer. The amorphous intermediate layer helps to relieve the strain in the accommodating buffer layer and, by doing so, aids in the growth of a high crystalline quality accommodating buffer layer.

Substrate 22, in accordance with an embodiment of the invention, is a monocrystalline semiconductor or compound semiconductor wafer, preferably of large diameter. The wafer can be of, for example, a material from Group IV of the periodic table. Examples of Group IV semiconductor materials include silicon, germanium, mixed silicon and germanium, mixed silicon and carbon, mixed silicon, germanium and carbon, and the like. Preferably substrate 22 is a wafer containing silicon or germanium, and most preferably is a high quality monocrystalline silicon wafer as used in the semiconductor industry. Substrate 22 may also include an epitaxial layer (not illustrated) to facilitate the fabrication of semiconductor devices as will be explained more fully below. Accommodating buffer layer 24 is preferably a monocrystalline oxide or nitride material epitaxially grown on the underlying substrate. In accordance with one embodiment of the invention, amorphous intermediate layer 28 is grown on substrate 22 at the interface between substrate 22 and the growing accommodating buffer layer by the oxidation of substrate 22 during the growth of layer 24. The amorphous intermediate layer serves to relieve strain that might otherwise occur in the monocrystalline accommodating buffer layer as a result of differences in the lattice constants of the substrate and the buffer layer. As used herein, lattice constant refers to the distance between atoms of a cell measured in the plane of the surface. If such strain is not relieved by the amorphous intermediate layer, the strain may cause defects in the crystalline structure of the accommodating buffer layer. Defects in the crystalline structure of the accommodating buffer layer, in turn, would make it difficult to achieve a high quality crystalline structure in monocrystalline material layer 26 which may comprise a semiconductor material, a compound semiconductor material, a monocrystalline oxide layer, or another type of material such as a metal or a non- metal.

Accommodating buffer layer 24 is preferably a monocrystalline oxide or nitride material selected for its crystalline compatibility with the underlying substrate and with the overlying material layer. For example, the material could be an oxide or nitride having a lattice structure closely matched to the substrate and to the subsequently applied monocrystalline material layer. Materials that are suitable for the accommodating buffer layer include metal oxides such as the alkaline earth metal/transition metal oxides such as alkaline earth metal titanates, alkaline earth metal zirconates, alkaline earth metal hafnates, alkaline earth metal tantalates, alkaline earth metal ruthenates, alkaline earth metal niobates, alkaline earth metal vanadates, alkaline earth metal tin-based perovskites, lanthanum aluminate, lanthanum scandium oxide, gadolinium oxide, other perovskite oxide materials, and other monocrystalline metal oxides. Additionally, various nitrides such as gallium nitride, aluminum nitride, and boron nitride may also be used for the accommodating buffer layer. Most of these materials are insulators, although strontium ruthenate, for example, is a conductor. Generally, these materials are metal oxides or metal nitrides, and more particularly, these metal oxide or nitrides typically, although not necessarily, include at least two different metallic elements. In some specific applications, the metal oxides or nitrides may include three or more different metallic elements.

Amorphous interface layer 28 is preferably an oxide formed by the oxidation of the surface of substrate 22, and more preferably is composed of a silicon oxide. The thickness of layer 28 is sufficient to relieve strain attributed to mismatches between the lattice constants of substrate 22 and accommodating buffer layer 24. Typically, layer 28 has a thickness in the range of approximately 0.5-5 nanometers (nm). As will be explained more fully below, in certain applications the thickness of the amorphous layer should be minimized, especially during the initial stages of the growth of the monocrystalline buffer layer.

The material for monocrystalline material layer 26 can be selected, as necessary, for a particular structure or application. For example, the monocrystalline material of layer 26 may comprise a compound semiconductor which can be selected, as needed for a particular semiconductor structure, from any of the Group IIIA and VA elements (III-V semiconductor compounds), mixed III-V compounds, Group II (A or B) and VIA elements (II- VI semiconductor compounds), mixed II- VI compounds, Group IV and VI elements (IV- VI semiconductor compounds), mixed IV- VI compounds, Group IV element (Group IV semiconductors), and mixed Group IV compounds. Examples include gallium arsenide (GaAs), gallium indium arsenide (GalnAs), gallium aluminum arsenide (GaAlAs), indium phosphide (InP), cadmium sulfide (CdS), cadmium mercury telluride (CdHgTe), zinc selenide (ZnSe), zinc sulfur selenide (ZnSSe), lead selenide (PbSe), lead telluride (PbTe), lead sulfide selenide (PbSSe), silicon (Si), germanium (Ge), silicon germanium (SiGe), silicon germanium carbide (SiGeC), and the like. However, monocrystalline material layer 26 may also comprise other semiconductor materials, monocrystalline oxides, metals, or non-metal materials which are used in the formation of semiconductor structures, devices and/or integrated circuits. Appropriate materials for template 30 are discussed below. Suitable template materials chemically bond to the surface of the accommodating buffer layer 24 at selected sites and provide sites for the nucleation of the epitaxial growth of monocrystalline material layer 26. When used, template layer 30 has a thickness ranging from about 1 to about 10 monolayers. Here a monolayer of a perovskite oxide, such as SrTiO , is defined as a layer of such an oxide having a thickness of its unit cell length along the growth direction. A monolayer of one of its components, such as a monolayer of Sr, is defined as the equivalent amount of atoms of this type, in this case the Sr atoms, contained in a monolayer of such an oxide. The template may also incorporate a wetting layer which helps to initiate high quality two dimensional crystalline growth.

FIG. 2 illustrates, in cross section, a portion of a semiconductor structure 40 in accordance with a further embodiment of the invention. Structure 40 is similar to the previously described semiconductor structure 20, except that an additional buffer layer 32 is positioned between accommodating buffer layer 24 and monocrystalline material layer 26. Specifically, the additional buffer layer is positioned between template layer 30 and the overlying layer of monocrystalline material. The additional buffer layer, formed of a semiconductor or compound semiconductor material when the monocrystalline material layer 26 comprises a semiconductor or compound semiconductor material, serves to provide a lattice compensation when the lattice constant of the accommodating buffer layer cannot be adequately matched to the overlying monocrystalline semiconductor or compound semiconductor material layer.

The structures and materials described above in connection with FIGS. 1 and 2 illustrate structures for growing monocrystalline material layers over a monocrystalline substrate. In some applications a monocrystalline material layer such as layer 26 is a necessary part of the device being fabricated. In other applications the accommodating buffer layer may become an integral part of the device being fabricated, such as a gate insulator of a field effect transistor. In such other applications the material layer formed overlying the monocrystalline accommodating buffer layer may or may not be monocrystalline. For example, as illustrated in FIG. 3, semiconductor structure 31 includes, in accordance with a further embodiment of the invention, a monocrystalline semiconductor substrate 22, amorphous intermediate layer 28, accommodating buffer layer 24, and overlying layer 33. The overlying layer may or may not be monocrystalline. For example, if semiconductor structure 31 is used in the fabrication of a field effect transistor, layer 33 may be polycrystalline silicon used for the fabrication of a gate electrode. Accommodating buffer layer 24, in such embodiment, could be used as a gate dielectric of the field effect transistor. Hence in such a structure, layer 24 is not an "accommodating buffer" as that term is used elsewhere in this disclosure, i.e., a monocrystalline layer providing an accommodation of underlying and overlying crystal lattice constants; but for sake of consistency, any monocrystalline layer grown overlying substrate 22 will be referred to by that term.

FIG. 4 schematically illustrates, in cross section, a portion of a semiconductor structure 34 in accordance with another exemplary embodiment of the invention. Structure 34 is similar to structure 20, except that structure 34 includes an amorphous layer 36, rather than accommodating buffer layer 24 and amorphous interface layer 28, and also includes an additional monocrystalline layer 38. As explained in greater detail below, amorphous layer 36 may be formed by first forming an accommodating buffer layer and an amorphous interface layer in a similar manner to that described above. Monocrystalline layer 38 is then formed (by epitaxial growth) overlying the monocrystalline accommodating buffer layer. The accommodating buffer layer then may be optionally exposed to an anneal process to convert at least a portion of the monocrystalline accommodating buffer layer to an amorphous layer. Amorphous layer 36 formed in this manner comprises materials from both the accommodating buffer and interface layers, which amorphous layers may or may not amalgamate. Thus, layer 36 may comprise one or two amorphous layers. Formation of amorphous layer 36 between substrate 22 and additional monocrystalline layer 26 (subsequent to layer 38 formation) relieves stresses between layers 22 and 38 and provides a true compliant substrate for subsequent processing— e.g., monocrystalline material layer 26 formation.

The processes previously described above in connection with FIGS. 1 -3 are adequate for growing monocrystalline material layers over a monocrystalline substrate. However, the process described in connection with FIG. 3, which includes transforming at least a portion of a monocrystalline accommodating buffer layer to an amorphous oxide layer, may be better for growing monocrystalline material layers because it allows any strain in layer 26 to relax.

Additional monocrystalline layer 38 may include any of the materials described throughout this application in connection with either of monocrystalline material layer 26 or additional buffer layer 32. For example, when monocrystalline material layer 26 comprises a semiconductor or compound semiconductor material, layer 38 may include monocrystalline Group IV, monocrystalline compound semiconductor materials, or other monocrystalline materials including oxides and nitrides.

In accordance with one embodiment of the present invention, additional monocrystalline layer 38 serves as an anneal cap during layer 36 formation and as a template for subsequent monocrystalline layer 26 formation. Accordingly, layer 38 is preferably thick enough to provide a suitable template for layer 26 growth (at least one monolayer) and thin enough to allow layer 38 to form as a substantially defect free monocrystalline material layer. In accordance with another embodiment of the invention, additional monocrystalline layer 38 comprises monocrystalline material (e.g., a material discussed above in connection with monocrystalline layer 26) that is thick enough to form devices within layer 38. In this case, a semiconductor structure in accordance with the present invention does not include monocrystalline material layer 26. In other words, the semiconductor structure in accordance with this embodiment includes only one monocrystalline layer disposed above amorphous oxide layer 36.

The following non-limiting, illustrative examples illustrate various combinations of materials useful in structures 20, 40, 31, and 34 in accordance with various alternative embodiments of the invention. These examples are merely illustrative, and it is not intended that the invention be limited to these illustrative examples.

Example 1

In accordance with one embodiment of the invention, monocrystalline substrate 22 is a silicon substrate, typically (100) oriented. The silicon substrate can be, for example, a silicon substrate having a diameter of about 200-300 mm as is commonly used in making complementary metal oxide semiconductor (CMOS) integrated circuits. In accordance with this embodiment of the invention, accommodating buffer layer 24 is a monocrystalline layer of Sr_zBaι_-zTiO where z ranges from 0 to 1 and the amorphous intermediate layer is a layer of silicon oxide (SiO_x) formed at the interface between the silicon substrate and the accommodating buffer layer. The value of z is selected to obtain one or more lattice constants closely matched to corresponding lattice constants of the underlying substrate and subsequently formed layer 26. The lattice structure of the resulting crystalline oxide exhibits a substantially 45 degree rotation with respect to the substrate silicon lattice structure. The accommodating buffer layer can have a thickness of about 2 to about 100 nanometers (nm) and preferably has a thickness of about 5 nm. In general, it is desired to have an accommodating buffer layer thick enough to isolate monocrystalline material layer 26 from the substrate to obtain the desired electrical and optical properties. Layers thicker than 100 nm usually provide little additional benefit while increasing cost unnecessarily; however, thicker layers may be fabricated if needed. The amorphous intermediate layer of silicon oxide can have a thickness of about 0.5-5 nm, and preferably a thickness of about 1 to 2 nm.

In accordance with this embodiment of the invention, monocrystalline material layer 26 is a compound semiconductor layer of gallium arsenide (GaAs) or aluminum gallium arsenide (AlGaAs) having a thickness of about 1 nm to about 100 micrometers (μm) and preferably having a thickness of about 0.5 μm to 10 μm. The thickness generally depends on the application for which the layer is being prepared. To facilitate the epitaxial growth of the gallium arsenide or aluminum gallium arsenide on the monocrystalline oxide, the oxide layer is capped with a template layer. The template layer preferably comprises one element of the compound semiconductor layer to react with the surface of the oxide layer that has been previously capped. The capping layer is preferably up to 3 monolayers of Sr-O, Ti- O, strontium or titanium. The template layer is preferably of Sr-Ga, Ti-Ga, Ti-As, Ti-O-As, Ti-O-Ga, Sr-O- As, Sr-Ga-O, Sr-Al-O, or Sr-Al. The thickness of the template layer is preferably about 0.5 to about 10 monolayers, and preferably about 0.5-3 monolayers. By way of a preferred example 0.5-3 monolayers of Ga deposited on a capped Sr-O terminated surface have been illustrated to successfully grow GaAs layers. To facilitate high quality two dimensional monocrystalline growth of layer 26, the template layer can also include a wetting layer on its upper surface. As explained more fully below, the wetting layer is formed of a material that changes the surface energy of the accommodating buffer layer to aid in the monocrystalline growth of the overlying layer. Suitable materials for the wetting layer include, for example, metals, intermetallics, and metal oxides having a cubic crystalline structure. Examples of such materials include NiAl, FeAl, CoAl, Ni, Co, Fe, Cu, Ag, Au, Ir, Rh, Pt, Pd, Rb, Cs, CoO, FeO, Cu₂O, Rb₂O₃, Cs₂O₃, and NiO. The thickness of the wetting layer is preferably 0.5-5.0 monolayers. Example 2

In accordance with a further embodiment of the invention, monocrystalline substrate 22 is a silicon substrate as described above. The accommodating buffer layer is a monocrystalline oxide of strontium or barium zirconate or hafnate in a cubic or orthorhombic phase with an amorphous intermediate layer of silicon oxide formed at the interface between the silicon substrate and the accommodating buffer layer. The accommodating buffer layer can have a thickness of about 2-100 nm and preferably has a thickness of at least 4 nm to ensure adequate crystalline and surface quality and is formed of a monocrystalline SrZrO₃, BaZrO , SrHfO , BaSnO₃ or BaHfO₃. For example, the accommodating buffer layer can be a monocrystalline oxide layer of BaZrO₃ grown at a temperature of about 700 degrees C. The lattice structure of the resulting crystalline oxide exhibits a 45 degree rotation with respect to the substrate silicon lattice structure. An accommodating buffer layer formed of these zirconate or hafnate materials is suitable for the growth of a monocrystalline material layer which comprises compound semiconductor materials in an indium phosphide (InP) system. In this system, the compound semiconductor material can be, for example, indium phosphide (InP), indium gallium arsenide (InGaAs), aluminum indium arsenide, (AlInAs), or aluminum gallium indium arsenide phosphide (AlGalnAsP), having a thickness of about 1.0 nm to 10 μm. A suitable template for this structure is about 0.5-10 monolayers and preferably about 0.5-2 monolayers of one of a material M-N or a material M-O-N, wherein M is selected from at least one of Zr, Hf, Ti, Sr, and Ba and N is selected from at least one of As, P, Ga, Al, and In. Alternatively, the template may comprise 0.5-10 monolayers of gallium (Ga), aluminum (Al), indium (In), or a combination of gallium, aluminum or indium, and preferably 0.5-2 monolayers of one of these materials. By way of an example, for a barium zirconate accommodating buffer layer, the surface is terminated with 0.5-2 monolayers of zirconium followed by deposition of 0.5-2 monolayers of arsenic to form a Zr-As template. As with the example above, the template layer may be completed with an appropriate wetting layer to facilitate the two dimensional monocrystalline growth of a subsequent layer. A monocrystalline layer of the compound semiconductor material from the indium phosphide system is then grown on the template layer. The resulting lattice structure of the compound semiconductor material exhibits a substantially 45 degree rotation with respect to the accommodating buffer layer lattice structure and a lattice mismatch between the buffer layer and (100) oriented InP of less than 2.5%, and preferably less than about 1.0%.

Example 3

In accordance with a further embodiment of the invention, a structure is provided that is suitable for the growth of an epitaxial film of a monocrystalline material comprising a II- VI material overlying a silicon substrate. The substrate is preferably a silicon wafer as described above. A suitable accommodating buffer layer material is Sr_xBaι_-xTiO₃, where x ranges from 0 to 1, having a thickness of about 2-100 nm and preferably a thickness of about 3-10 nm. The monocrystalline II- VI compound semiconductor material grown epitaxially overlying the accommodating buffer layer can be, for example, zinc selenide (ZnSe) or zinc sulfur selenide (ZnSSe). A suitable template for this material system includes 0.5-10 monolayers of zinc-oxygen (Zn-O) followed by 0.5-2 monolayers of an excess of zinc followed by the selenidation of zinc on the surface. Alternatively, a template can be, for example, 0.5-10 monolayers of strontium-sulfur (Sr-S) followed by the ZnSSe. Again, the template can also include an appropriate wetting layer.

Example 4

This embodiment of the invention is an example of structure 40 illustrated in FIG. 2. Substrate 22, accommodating buffer layer 24, and monocrystalline material layer 26 can be similar to those described in example 1. In addition, an additional buffer layer 32 serves to alleviate any strains that might result from a mismatch between the crystal lattice of the accommodating buffer layer and the lattice of the monocrystalline material. Buffer layer 32 can be a layer of germanium or a GaAs, an aluminum gallium arsenide (AlGaAs), an indium gallium phosphide (InGaP), an aluminum gallium phosphide (AlGaP), an indium gallium arsenide (InGaAs), an aluminum indium phosphide (AllnP), a gallium arsenide phosphide (GaAsP), or an indium gallium phosphide (InGaP) strain compensated superlattice. In accordance with one aspect of this embodiment, buffer layer 32 includes a GaAs_xPι__x superlattice, wherein the value of x ranges from 0 to 1. In accordance with another aspect, buffer layer 32 includes an In_yGa_1-yP superlattice, wherein the value of y ranges from 0 to 1. By varying the value of x or y, as the case may be, the lattice constant is varied from bottom to top across the superlattice to create a substantial (i.e., effective) match between lattice constants of the underlying oxide and the overlying monocrystalline material which, in this example, is a compound semiconductor material. The compositions of other compound semiconductor materials, such as those listed above, may also be similarly varied to manipulate the lattice constant of layer 32 in a like manner. The superlattice can have a thickness of about 50-500 nm and preferably has a thickness of about 100-200 nm. The superlattice period can have a thickness of about 2-15 nm, preferably, 2-10 nm. The template for this structure can be the same of that described in Example 1.

Alternatively, buffer layer 32 can be a layer of monocrystalline germanium having a thickness of 1-50 nm and preferably having a thickness of about 2-20 nm. In using a germanium buffer layer, a template layer of either germanium-strontium (Ge-Sr) or germanium-titanium (Ge-Ti) having a thickness of about 0.5-2 monolayers can be used as a nucleating site for the subsequent growth of the monocrystalline germanium layer. The formation of the accommodating buffer layer is capped with either 0.5-1 monolayer of strontium or 0.5-1 monolayer of titanium to act as a nucleating site for the subsequent growth of the monocrystralline germanium layer. The layer of strontium or titanium provides a nucleating site to which the first monolayer of germanium can bond. The same wetting agents described above in Example 1 can be used to initiate high quality two dimensional growth of the germanium layer.

Example 5

This example also illustrates materials useful in a structure 40 as illustrated in FIG. 2. Substrate material 22, accommodating buffer layer 24, monocrystalline material layer 26 and template layer 30 can be the same as those described above in Example 2. In addition, additional buffer layer 32 is inserted between the accommodating buffer layer and the overlying monocrystalline material layer. The buffer layer, a further monocrystalline material which, in this example, comprises a semiconductor material, can be, for example, a graded layer of indium gallium arsenide (InGaAs) or indium aluminum arsenide (InAlAs). In accordance with one aspect of this embodiment, additional buffer layer 32 includes InGaAs in which the indium in the composition varies from 0 at the monocrystalline material layer 26 to about 50% at the accommodating buffer layer 24. The additional buffer layer 32 preferably has a thickness of about 10-30 nm. Varying the composition of the buffer layer from GaAs to InGaAs serves to provide a substantial (i.e., effective) lattice match between the underlying monocrystalline oxide material and the overlying layer of monocrystalline material which, in this example, is a compound semiconductor material. Such a buffer layer is especially advantageous if there is a lattice mismatch between accommodating buffer layer 24 and monocrystalline material layer 26.

Example 6

This example provides exemplary materials useful in structure 31 , as illustrated in FIG. 3. Substrate material 22 is, for example, a monocrystalline silicon wafer as commonly used in the semiconductor industry for the fabrication of semiconductor devices and integrated circuits. Depending on the device or integrated circuit to be fabricated, the substrate may be a bulk wafer or it may be a bulk wafer having an epitaxial silicon layer formed on the top surface thereof. Impurity doped regions may be formed in the substrate as, for example, source and drain regions of a field effect transistor. Amorphous intermediate layer 28 is a silicon oxide formed by the oxidation of the surface of the silicon substrate. Accommodating buffer layer 24 is a monocrystalline layer of strontium titanate having an initial thickness of 1-10 monolayers, and preferably an initial thickness of 3-6 monolayers. Layer 33 formed overlying the accommodating buffer layer is a layer of polycrystalline silicon from which a gate electrode of the field effect transistor will be formed. The layer of strontium titanate serves as a gate dielectric of the transistor. In an alternate embodiment, layer 33 can be a layer of monocrystalline strontium zirconate to form a so called "medium k" gate dielectric of the transistor. A gate electrode would then be formed overlying the strontium zirconate dielectric layer. In the fabrication of semiconductor structure 31, it may be advantageous to minimize the thickness of amorphous intermediate layer 28. The amorphous intermediate layer is one component of the gate dielectric of the field effect transistor, and it is usually desirable to minimize that dielectric thickness. Additionally, the silicon oxide that forms the amorphous intermediate layer is also a relatively "low k" dielectric and is thus to be minimized.

Example 7

This example provides exemplary materials useful in structure 34, as illustrated in FIG. 4. Substrate material 22, template layer 30, and monocrystalline material layer 26 may be the same as those described above in connection with example 1.

Amorphous layer 36 is an amorphous oxide layer which is suitably formed of a combination of amorphous intermediate layer materials (e.g., layer 28 materials as described above) and accommodating buffer layer materials (e.g., layer 24 materials as described above). For example, amorphous layer 36 may include a combination of SiO_x and Sr_zBaι_-zTiO₃ (where z ranges from 0 to 1) which combine or mix, at least partially, during an anneal process to form amorphous oxide layer 36. The thickness of amorphous layer 36 may vary from application to application and may depend on such factors as desired insulating properties of layer 36, type of monocrystalline material comprising layer 26, and the like. In accordance with one exemplary aspect of the present embodiment, layer 36 thickness is about 1 nm to about 100 nm, preferably about 1-10 nm, and more preferably about 3-5 nm.

Layer 38 comprises a monocrystalline material that can be grown epitaxially over a monocrystalline oxide material such as the material used to form accommodating buffer layer 24. In accordance with one embodiment of the invention, layer 38 includes the same materials as those comprising layer 26. For example, if layer 26 includes GaAs, layer 38 also includes GaAs. However, in accordance with other embodiments of the present invention, layer 38 may include materials different from those used to form layer 26. In accordance with one exemplary embodiment of the invention, layer 38 if formed to a thickness of about 1 nm to about 500 nm.

Referring again to FIGS. 1 - 4, substrate 22 is a monocrystalline substrate such as, for example, a monocrystalline silicon or gallium arsenide substrate. The crystalline structure of the monocrystalline substrate is characterized by a lattice constant and by a lattice orientation. In similar manner, accommodating buffer layer 24 is also a monocrystalline material and the lattice of that monocrystalline material is characterized by a lattice constant and a crystal orientation. The lattice constants of the accommodating buffer layer and the monocrystalline substrate must be closely matched or, alternatively, must be such that upon rotation of one crystal orientation with respect to the other crystal orientation, a substantial match in lattice constants is achieved. In this context the terms "substantially equal" and "substantial match" mean that there is sufficient similarity between the lattice constants to permit the growth of a high quality crystalline layer on the underlying layer. FIG. 5 illustrates graphically the relationship of the achievable thickness of a grown crystal layer of high crystalline quality as a function of the mismatch between the lattice constants of the host crystal and the grown crystal. Curve 42 illustrates the boundary of achievable high crystalline quality material. The area to the right of curve 42 represents layers that have a large number of defects. With no lattice mismatch, it is theoretically possible to grow an infinitely thick, high quality epitaxial layer on the host crystal. As the mismatch in lattice constants increases, the thickness of achievable, high quality crystalline layer decreases rapidly. As a reference point, for example, if the lattice constants between the host crystal and the grown layer are mismatched by more than about 2%, monocrystalline epitaxial layers in excess of about 20 nm cannot be achieved.

In accordance with one embodiment of the invention, substrate 22 is a (100) oriented monocrystalline silicon wafer and accommodating buffer layer 24 is a layer of strontium barium titanate. Substantial (i.e., effective) matching of lattice constants between these two materials is achieved by rotating the crystal orientation of the titanate material by approximately 45° with respect to the crystal orientation of the silicon substrate wafer. The inclusion in the structure of amorphous interface layer 28, a silicon oxide layer in this example, if it is of sufficient thickness, serves to reduce strain in the monocrystalline titanate layer that might result from any mismatch in the lattice constants of the host silicon wafer and the grown titanate layer. As a result, in accordance with an embodiment of the invention, a high quality, thick, monocrystalline titanate layer is achievable.

Still referring to FIGS. 1 - 4, layer 26 is a layer of epitaxially grown monocrystalline material and that crystalline material is also characterized by a crystal lattice constant and a crystal orientation. In accordance with one embodiment of the invention, the lattice constant of layer 26 differs from the lattice constant of substrate 22. To achieve high crystalline quality in this epitaxially grown monocrystalline layer, the accommodating buffer layer must be of high crystalline quality. In addition, in order to achieve high crystalline quality in layer 26, substantial matching between the crystal lattice constant of the host crystal, in this case, the monocrystalline accommodating buffer layer, and the grown crystal layer is desired. With properly selected materials this substantial matching of lattice constants is achieved as a result of rotation of the crystal orientation of the grown crystal with respect to the orientation of the host crystal. For example, if the grown crystal is gallium arsenide, aluminum gallium arsenide, zinc selenide, or zinc sulfur selenide and the accommodating buffer layer is monocrystalline Sr_xBaι_-xTiO , substantial matching of crystal lattice constants of the two materials is achieved, wherein the crystal orientation of the grown layer is rotated by substantially 45° with respect to the orientation of the host monocrystalline oxide. Similarly, if the host material is a strontium or barium zirconate or a strontium or barium hafnate or barium tin oxide and the compound semiconductor layer is indium phosphide or gallium indium arsenide or aluminum indium arsenide, substantial matching of crystal lattice constants can be achieved by rotating the orientation of the grown crystal layer by 45° with respect to the host oxide crystal. In some instances, a crystalline semiconductor buffer layer 32 between the host oxide and the grown monocrystalline material layer can be used to reduce strain in the grown monocrystalline material layer that might result from small differences in lattice constants. Better crystalline quality in the grown monocrystalline material layer can thereby be achieved.

The following example illustrates a process, in accordance with one embodiment of the invention, for fabricating a semiconductor structure such as the structures depicted in FIGS. 1 - 4. The process starts by providing a monocrystalline semiconductor substrate comprising silicon or germanium. In accordance with a preferred embodiment of the invention, the semiconductor substrate is a silicon wafer having a (100) orientation. The substrate is oriented on axis or, if desired, up to 8° off axis towards a desired crystallographic direction. At least a portion of the semiconductor substrate has a bare surface, although other portions of the substrate, as described below, may encompass other structures. The term "bare" in this context means that the surface in that portion of the substrate has been cleaned to remove any oxides, contaminants, or other foreign material. As is well known, bare silicon is highly reactive and readily forms a native oxide. The term "bare" is intended to encompass such a native oxide. In accordance with one embodiment of the invention, a thin silicon oxide is then intentionally grown on the semiconductor substrate. The thin silicon oxide is grown immediately prior to the formation of the monocrystalline accommodating buffer layer, and can be grown by thermal or chemical oxidation of the silicon surface. In accordance with one embodiment of the invention, the thin silicon oxide is grown by exposing the substrate surface to an ultraviolet (UV) lamp in the presence of ozone for a time period of up to about 20 minutes. The wafer is initially at ambient room temperature, but is heated by the UV lamp to a temperature of between 20°C and 100°C by the end of the treatment. Alternatively, in accordance with a further embodiment of the invention, the semiconductor substrate can be exposed to an rf or an ECR oxygen plasma. During such treatment the temperature of the substrate is maintained at a temperature of between 100°C and 600°C with an oxygen partial pressure of 10^"5 to 10^"8 millibar (mbar). In accordance with yet another embodiment of the invention, the thin silicon oxide can be grown by exposing the substrate to an ozone ambient at an elevated temperature in the same processing apparatus, such as a molecular beam epitaxial (MBE) reactor, used for the subsequent deposition of the accommodating buffer layer. Use of an ozone treatment to grow the oxide has the beneficial effect of removing carbon contamination from the surface of the substrate. In order to epitaxially grow a monocrystalline oxide layer overlying the monocrystalline substrate, the native and or grown oxide layer must first be removed to expose the crystalline structure of the underlying substrate. The following process is preferably carried out by molecular beam epitaxy, although other epitaxial processes may also be used in accordance with the present invention. The native oxide can be removed by first depositing a thin layer (preferably 1-3 monolayers) of strontium, barium, a combination of strontium and barium, or other alkaline earth metals or combinations of alkaline earth metals onto the substrate in an MBE apparatus. In the case where strontium is used, the substrate is then heated to a temperature above 720° C as measured by an optical pyrometer to cause the strontium to react with the native and/or grown silicon oxide layer. The strontium serves to reduce the silicon oxide to leave a silicon oxide-free surface. The resultant surface may exhibit an ordered 2x1 structure. If an ordered (2x1) reconstruction has not been achieved at this stage of the process, the structure may be exposed to additional strontium until an ordered (2x1) reconstruction is obtained. The ordered 2x1 reconstruction forms a template for the ordered growth of an overlying layer of a monocrystalline oxide. The template provides the necessary chemical and physical properties to nucleate the crystalline growth of an overlying layer.

It is understood that precise measurement of actual temperatures in MBE equipment, as well as other processing equipment, is difficult, and is commonly accomplished by the use of a pyrometer or by means of a thermocouple placed in close proximity to the substrate. Calibrations can be performed to correlate the pyrometer temperature reading to that of the thermocouple. However, neither temperature reading is necessarily a precise indication of actual substrate temperature. Furthermore, variations may exist when measuring temperatures from one MBE system to another MBE system. For the purpose of this description, typical pyrometer temperatures will be used, and it should be understood that variations may exist in practice due to these measurement difficulties.

In accordance with an alternate embodiment of the invention, the native and/or grown silicon oxide can be converted and the substrate surface can be prepared for the growth of a monocrystalline oxide layer by depositing an alkaline earth metal oxide, such as strontium oxide, strontium barium oxide, or barium oxide, onto the substrate surface by MBE at a low temperature and by subsequently heating the structure to a temperature above 720°C. At this temperature a solid state reaction takes place between the strontium oxide and the native and/or grown silicon oxide causing the reduction of the silicon oxide and leaving an ordered 2x1 reconstruction on the substrate surface. If an ordered (2x1) reconstruction has not been achieved at this stage of the process, the structure may be exposed to additional strontium until an ordered (2x1) reconstruction is obtained. Again, this forms a template for the subsequent growth of an ordered monocrystalline oxide layer. In either method for removing the silicon oxide layer and preparing the surface for the subsequent formation of a monocrystalline accommodating buffer layer, surface reconstruction can be monitored in real time, for example by using reflection high energy electron diffraction (RHEED). Other well known real time monitoring techniques may also be used. Following the removal of the silicon oxide and formation of a template layer on the surface of the substrate, growth of a monocrystalline oxide layer on the substrate can begin. This growth is accomplished in the same apparatus, preferably an MBE reactor, as is the surface preparation. During the growth of the monocrystalline oxide layer overlying the monocrystalline silicon substrate, reactants, including oxygen, are introduced to the MBE reactor. Under proper conditions the reactants react at the silicon surface to grow the desired monocrystalline oxide. Because of the presence of the oxygen, however, a competing reaction, that of oxidizing the silicon substrate, can also occur. To achieve a high quality two dimensional growth of the monocrystalline oxide layer, the growth process should be controlled to suppress the competing reaction of the oxygen with the silicon substrate, a reaction that causes oxidation of the silicon substrate and disrupts the ordered two dimensional growth of the monocrystalline oxide layer. Although a layer of amorphous oxide underlying the monocrystalline oxide layer may be desirable for reducing strain in the monocrystalline oxide layer, that amorphous layer must be grown after the monocrystalline growth has been sufficiently initiated. In accordance with one embodiment of the invention, the ordered two dimensional growth of a high quality monocrystalline oxide layer, such as a layer of monocrystalline strontium titanate, overlying an oxidizable monocrystalline substrate, such as a silicon substrate, can be accomplished by the following process. The inventive process suppresses the oxidation of the substrate material (i.e., in the case of a silicon substrate, oxidation of the silicon substrate to grow an amorphous silicon oxide layer) while allowing the oxidation of strontium and titanium to grow monocrystalline strontium titanate.

Following the removal of the silicon oxide layer from the substrate surface and formation of a template layer in a manner such as that described above, the substrate is cooled to a temperature between room temperature and about 400°C, and preferably to a temperature of about 300°C or less. The initial growth of the strontium titanate monocrystalline layer will take place at this lowered temperature. At the lowered temperature the oxidation of strontium and titanium to form strontium titanate is favored over the oxidation of the silicon substrate. The higher the temperature, the greater the oxidation rate of both the silicon and the strontium titanate components. Similarly, the higher the partial pressure of oxygen in the reactor, the greater the oxidation rate of both the silicon substrate and the strontium titanate components strontium and titanium. However, the oxidation of strontium and titanium at low temperatures and at appropriate low oxygen partial pressures is favored in contrast to the oxidation of silicon. Accordingly, to facilitate the growth of the strontium titanate in the most efficient manner, the temperature selected should be as high as possible without incurring deleterious amounts of silicon oxidation. Once the lowered temperature is stabilized, oxygen is introduced into the reactor to establish a partial pressure of oxygen in the reactor of between about 1 x 10^"8 mbar and about 3 x 10^"7 mbar. The exact pressure selected will depend on some physical parameters of the reactor such as the size of the reactor chamber and the reactor pumping capacity. The partial pressure selected should be high enough to grow stoichiometric strontium titanate but not too high to cause significant oxidation of Si The strontium and titanium shutters of the MBE reactor are then opened to introduce strontium and titanium to the reaction. The ratio of strontium and titanium is adjusted to approximately 1 : 1 to grow stoichiometric strontium titanate. After about 1-3 monolayers of strontium titanate are grown on the silicon substrate surface the shutters are closed and the oxygen flow is terminated to reduce the oxygen partial pressure in the reactor chamber to less than about 5 x 10^"9 mbar. Under the above conditions the 1-3 monolayers of strontium titanate form on the silicon surface as an ordered two dimensional monocrystalline layer without significant oxidation of the silicon surface. Grown at 300°C, the order parameter of the strontium titanate layer is not high. That is, the film, although monocrystalline, is not of high crystalline quality. The temperature of the substrate is then raised to about 500 - 750°C and preferably to about 650°C to anneal the monocrystalline strontium titanate layer and to thereby improve the crystalline quality of the layer. At this elevated temperature the titanate layer becomes much more ordered. The ordering of the layer can be monitored in real time, preferably by observing RHEED patterns from the surface. The substrate is maintained at the elevated temperature until the intensity of the RHEED pattern begins to flatten out. This indicates that the ordering of the monocrystalline strontium titanate layer has saturated. The anneal at the elevated temperature, preferably less than 15 minutes is terminated after the saturation is observed. Following the annealing process, the temperature of the substrate is again reduced and the growth process is initiated again. Because the silicon surface is not exposed, but is covered by the initial 1-3 monolayers of titanate, the growth temperature can be raised, for example to 400°C. Once the substrate reaches the lowered temperature (preferably between about 300°C and about 400°C), oxygen is again introduced into the reactor chamber and the partial pressure of oxygen is set to a value equal to or greater than the partial pressure maintained during the previous deposition. The titanium and strontium shutters are opened and an additional 1-3 monolayers of monocrystalline strontium titanate are grown overlying the silicon substrate. The additional strontium titanate can then be annealed, as above, to improve the crystallinity of the layer. Again, effects of the annealing on the crystallinity of the layer can be monitored real time by RHEED. The steps of growth followed by anneal can be repeated to increase the thickness of the monocrystalline oxide layer. After a monocrystalline strontium titanate layer having a thickness greater than about 5 monolayers and preferably greater than about 10 monolayers has been grown on the silicon substrate, the silicon substrate will be sufficiently isolated from the reactants and additional monocrystalline strontium titanate (if additional strontium titanate is necessary for the device structure being fabricated) can be grown at a higher temperature. For example, additional strontium titanate can be grown at a temperature between about 550°C and about 950°C and preferably at a temperature greater than about 650°C. Additionally, after the thickness of the monocrystalline strontium titanate layer exceeds about 10 monolayers, the partial pressure of oxygen can be increased above the initial minimum value to cause the growth of an amorphous silicon oxide layer at the interface between the monocrystalline silicon substrate and the monocrystalline strontium titanate layer. This silicon oxidation step may be applied either during or after the growth of the strontium titanate layer. The growth of the silicon oxide layer results from the diffusion of oxygen through the strontium titanate layer to the interface where the oxygen reacts with silicon at the surface of the underlying substrate. The strontium titanate grows as an ordered (100) monocrystal with the (100) crystalline orientation rotated by 45° with respect to the underlying substrate. Strain that otherwise might exist in the strontium titanate layer because of the small mismatch in lattice constant between the silicon substrate and the growing crystal is relieved by the presence of the amorphous silicon oxide intermediate layer. In the foregoing, a process has been disclosed for growing a high quality monocrystalline strontium titanate layer on a silicon substrate. Other monocrystalline oxides, and specifically metal oxides, can be grown on monocrystalline substrates in similar manner by oxidizing the metal without oxidizing the underlying substrate. This includes a series oxides such as SrZrO , BaTiO₃, Pb(Zr, Ti)O₃, (Pb, La)(Zr, Ti)O₃, LaAlO₃, SrRuO₃, YBCO, CeO₂, ZrO₂, and MgO etc. The principles of initiating growth at a low temperature to prevent the oxidization of the substrate and then anneal without the presence of the oxidant to improve the crystallinity at a small film thickness can be applied to any other oxides on any oxidizable substrates. In addition, the oxidants are not limited to oxygen but can be any other reactants that oxidize the substrate, such as O₃, H₂O, N₂O, N₂, F₂, Cl₂, etc. The monocrystalline oxide grown in this manner overlying a monocrystalline substrate can be used as a starting material for many device structures. For example, without going into great detail, a monocrystalline oxide such as strontium titanate may be used by itself as a high dielectric constant ("high k") insulator of a field effect transistor. In such a device a thin monocrystalline layer with a minimum of amorphous silicon oxide may be desired. Other field effect devices may be formed in which the strontium titanate layer is used as an accommodating buffer layer for the growth of a medium k dielectric such as monocrystalline strontium zirconate. Monocrystalline strontium zirconate is difficult to grow on monocrystalline silicon, but can be grown on strontium titanate by a MBE process or by a sol-gel process. The monocrystalline strontium titanate layer can also be used as an accommodating buffer layer for forming other monocrystalline insulator layers such as PZT, PLZT, conducting layers such as SrRuO₃, (La, Sr)CoO₃, superconducting layers such as YBCO, BSCCO, binary oxides such as MgO, ZrO₂, and even thick layers of strontium titanate. All of these can be formed on the monocrystalline strontium titanate by MBE, CBE, CVD, PVD, PLD , sol-gel process or by one of the other epitaxial growth processes described elsewhere in this disclosure. Other processes in which a monocrystalline accommodating buffer layer is formed on a monocrystalline substrate and a monocrystalline layer is formed on that accommodating buffer layer are described below in greater detail. After the strontium titanate layer has been grown to the desired thickness, the monocrystalline strontium titanate may be capped by a template layer that is conducive to the subsequent growth of an epitaxial layer of a desired monocrystalline material. For example, for the subsequent growth of a monocrystalline compound semiconductor material layer of gallium arsenide, the MBE growth of the strontium titanate monocrystalline layer can be capped by terminating the growth with up to 2 monolayers of titanium, up to 2 monolayers of titanium-oxygen or with up to 2 monolayers of strontium-oxygen. Following the formation of this capping layer, arsenic is deposited to form a Ti-As bond, a Ti-O- As bond or a Sr-O- As bond. Any of these form an appropriate template for deposition and formation of a monocrystalline gallium arsenide layer. Following the formation of the template, gallium is subsequently introduced to react with the arsenic to form gallium arsenide. Alternatively, up to 3 monolayer of gallium can be deposited on the capping layer to form a Sr-O-Ga bond, a Ti-Ga bond, or a Ti-O-Ga bond; arsenic is subsequently introduced with the gallium to form the GaAs.

In accordance with a further embodiment of the invention, before growth of the GaAs layer, the template layer is enhanced by adding a wetting layer to the top thereof. Without the wetting layer, three dimensional growth of the compound semiconductor layer often occurs at the initial nucleation stage. The occurrence of three dimensional growth results from low surface and interface energies associated with the oxide surface (in this example the strontium titanate surface). Oxides are typically chemically and energetically more stable than metals and most electronic materials such as GaAs. The three dimensional growth results in the spotty localized growth of discrete GaAs patches. Upon further growth the patches may grow together, but not as a monocrystalline layer. To facilitate the desired two dimensional growth, a wetting layer may be epitaxially grown on the upper surface of the accommodating buffer layer to raise the surface energy at the surface of the oxide layer. Useful wetting agents include materials having a cubic crystalline structure selected from the group of metals, intermetallics, and metal oxides. Representative materials meeting these criteria include NiAl, FeAl, CoAl, Ni, Co, Fe, Cu, Ag, Au, Ir, Rh, Pt, Pd, Rb, Cs, CoO, FeO, Cu₂O, Rb₂O₃, Cs₂O₃, and NiO. The selected wetting agent is deposited to a thickness of 0.5 - 5.0 monolayers on and as part of the template layer in the same process apparatus used for the deposition of the accommodating buffer layer. For example, if the accommodating buffer layer is strontium titanate, barium titanate, or barium stontium titanate and the desired monocrystalline compound semiconductor layer is GaAs or AlGaAs, 0.5 - 5.0 monolayers of NiAl form a suitable wetting layer. Preferably the deposition of the NiAl is initiated with the deposition of Ni.

In accordance with yet another embodiment of the invention, a non- monocrystalline layer such as a layer of polycrystalline silicon may be deposited over the moncrystalline oxide accommodating buffer layer. In such an embodiment, the monocrystalline accommodating buffer layer and any monocrystalline oxide layer formed thereover may be used, for example, as the gate insulator of an insulated gate field effect transistor. The polycrystalline silicon or other non- monocrystalline layer may be used, for example, to form the gate electrode of the field effect transistor. FIG. 6 is a high resolution Transmission Electron Micrograph (TEM) of semiconductor material manufactured in accordance with one embodiment of the present invention. Single crystal SrTiO₃ accommodating buffer layer 24 was grown epitaxially on silicon substrate 22. During this growth process, an amorphous interfacial layer 28 was formed which relieves strain due to lattice mismatch. GaAs compound semiconductor layer 26 was then grown epitaxially using template layer 30.

FIG. 7 illustrates an x-ray diffraction spectrum taken on a structure including GaAs monocrystalline layer 26 comprising GaAs grown on silicon substrate 22 using accommodating buffer layer 24. The peaks in the spectrum indicate that both accommodating buffer layer 24 and GaAs compound semiconductor layer 26 are single crystal and (100) orientated.

The structure illustrated in FIG. 2 can be formed by the process discussed above with the addition of an additional buffer layer deposition step. Additional buffer layer 32 is formed overlying the template layer before the deposition of monocrystalline material layer 26. If the additional buffer layer is a monocrystalline material comprising a compound semiconductor superlattice, such a superlattice can be deposited, for example by MBE, on template 30, optionally including a wetting layer, as described above. If instead the additional buffer layer is a monocrystalline material layer comprising a layer of germanium, the process above is modified to cap the strontium titanate monocrystalline layer with a final layer of either strontium or titanium and then optionally depositing a wetting layer formed of one of the wetting agents described above. The germanium buffer layer then can be deposited directly on this template/wetting layer.

Structure 34, illustrated in FIG. 4, may be formed by growing an accommodating buffer layer 24, forming an amorphous oxide layer 28 over substrate 22, and growing semiconductor layer 38 over the accommodating buffer layer, as described above. The accommodating buffer layer and the amorphous oxide layer are then exposed to an anneal process sufficient to change the crystalline structure of the accommodating buffer layer from monocrystalline to amorphous, thereby forming an amorphous layer such that the combination of the amorphous oxide layer and the now amorphous accommodating buffer layer form a single amorphous oxide layer 36. Layer 26 is then subsequently grown over layer 38. Alternatively, the anneal process may be carried out subsequent to growth of layer 26.

In accordance with one aspect of this embodiment, layer 36 is formed by exposing substrate 22, accommodating buffer layer 24, amorphous oxide layer 28, and monocrystalline layer 38 to a rapid thermal anneal process with a peak temperature of about 700°C to about 1000°C (actual temperature) and a process time of about 5 seconds to about 20 minutes. However, other suitable anneal processes may be employed to convert the accommodating buffer layer to an amorphous layer in accordance with the present invention. For example, laser annealing, electron beam annealing, or "conventional" thermal annealing processes (in the proper environment) may be used to form layer 36. When conventional thermal annealing is employed to form layer 36, an overpressure of one or more constituents of layer 38 may be required to prevent degradation of that layer during the anneal process. For example, when layer 38 includes GaAs, the anneal environment preferably includes an overpressure of arsenic to mitigate degradation of layer 38. Alternately, an appropriate anneal cap, such as silicon nitride, may be utilized to prevent the degradation of layer 38 during the anneal process with the anneal cap being removed after the annealing process. As noted above, layer 38 of structure 34 may include any materials suitable for either of layers 32 or 26. Accordingly, any deposition or growth methods described in connection with either layer 32 or 26 may be employed to deposit layer 38. FIG. 8 is a high resolution TEM of semiconductor material manufactured in accordance with the embodiment of the invention illustrated in FIG. 4. In accordance with this embodiment, a single crystal SrTiO₃ accommodating buffer layer was grown epitaxially on silicon substrate 22. During this growth process, an amorphous interfacial layer was formed as described above. Next, additional monocrystalline layer 38 comprising a compound semiconductor layer of GaAs was formed above the accommodating buffer layer and the accommodating buffer layer was exposed to an anneal process to form amorphous oxide layer 36.

FIG. 9 illustrates an x-ray diffraction spectrum taken on a structure including additional monocrystalline layer 38 comprising a GaAs compound semiconductor layer and amorphous oxide layer 36 formed on silicon substrate 22. The peaks in the spectrum indicate that GaAs compound semiconductor layer 38 is single crystal and (100) orientated and the lack of peaks around 40 to 50 degrees indicates that layer 36 is amorphous.

The process described above illustrates a process for forming a semiconductor structure including a silicon substrate, an overlying oxide layer, and a monocrystalline material layer comprising a gallium arsenide compound semiconductor layer by the process of molecular beam epitaxy. The process can also be carried out by the process of chemical vapor deposition (CVD), metal organic chemical vapor deposition (MOCVD), migration enhanced epitaxy (MEE), atomic layer epitaxy (ALE), physical vapor deposition (PVD), chemical solution deposition (CSD), pulsed laser deposition (PLD), or the like. Further, by a similar process, other monocrystalline accommodating buffer layers such as alkaline earth metal titanates, zirconates, hafnates, tantalates, vanadates, ruthenates, and niobates, alkaline earth metal tin-based perovskites, other perovskites, lanthanum aluminate, lanthanum scandium oxide, gadolinium oxide, and other metal oxides can also be grown. Further, by a similar process such as MBE, other monocrystalline material layers comprising other III-V, II- VI, and IV-VI monocrystalline compound semiconductors, semiconductors, metals and non-metals can be deposited overlying the monocrystalline oxide accommodating buffer layer.

Each of the variations of monocrystalline material layer and monocrystalline oxide accommodating buffer layer uses an appropriate template for initiating the growth of the monocrystalline material layer. For example, if the accommodating buffer layer is an alkaline earth metal zirconate, the oxide can be capped by a thin layer of zirconium. The deposition of zirconium can be followed by the deposition of arsenic or phosphorus to react with the zirconium as a precursor to depositing indium gallium arsenide, indium aluminum arsenide, or indium phosphide, respectively. Similarly, if the monocrystalline oxide accommodating buffer layer is an alkaline earth metal hafnate, the oxide layer can be capped by a thin layer of hafnium. The deposition of hafnium is followed by the deposition of arsenic or phosphorous to react with the hafnium as a precursor to the growth of an indium gallium arsenide, indium aluminum arsenide, or indium phosphide layer, respectively. In a similar manner, strontium titanate can be capped with a layer of strontium or strontium and oxygen, and barium titanate can be capped with a layer of barium or barium and oxygen. Each of these depositions can be followed by the deposition of arsenic or phosphorus to react with the capping material to form a template for the deposition of a monocrystalline material layer comprising compound semiconductors such as indium gallium arsenide, indium aluminum arsenide, or indium phosphide.

Single crystal silicon has 4-fold symmetry. That is, its structure is essentially the same as it is rotated in 90 degree steps in the plane of the (100) surface. Likewise, strontium titanate and many other oxides have a 4-fold symmetry. On the other hand, GaAs and related compound semiconductors have a 2-fold symmetry. The 0 degree and 180 degree rotations of the 2-fold symmetry are not the same as the 90 degree and 270 degree rotations of the 4-fold symmetry. If GaAs is nucleated upon strontium titanate at multiple locations on the surface, two different phases are produced. As the material continues to grow, the two phases meet and form anti- phase domains. These anti-phase domains can have an adverse effect upon certain types of devices, particularly minority carrier devices like lasers and light emitting diodes. In accordance with one embodiment of the present invention, in order to provide for the formation of high quality monocrystalline compound semiconductor material, the starting substrate is off-cut or misoriented from the ideal (100) orientation by 0.5 to 6 degrees in any direction, and preferably 1 to 2 degrees toward the [110] direction. This offcut provides for steps or terraces on the silicon surface and it is believed that these substantially reduce the number of anti-phase domains in the compound semiconductor material, in comparison to a substrate having an offcut near 0 degrees or off cuts larger than 6 degrees. The greater the amount of off-cut, the closer the steps and the smaller the terrace widths become. At very small angles, nucleation occurs at other than the step edges, decreasing the size of single phase domains. At high angles, smaller terraces decrease the size of single phase domains. Growing a high quality oxide, such as strontium titanate, upon a silicon surface causes surface features to be replicated on the surface of the oxide. The step and terrace surface features are replicated on the surface of the oxide, thus preserving directional cues for subsequent growth of compound semiconductor material.

Because the formation of the amorphous interface layer occurs after the nucleation of the oxide has begun, the formation of the amorphous interface layer does not disturb the step structure of the oxide.

After the growth of an appropriate accommodating buffer layer, such as strontium titanate or other materials as described earlier, a template layer is used to promote the proper nucleation of compound semiconductor material. In accordance with one embodiment, the strontium titanate is capped with up to 2 monolayers of SrO. The template layer 30 for the nucleation of GaAs is formed by raising the substrate to a temperature in the range of 540°C to 630°C and exposing the surface to gallium. The amount of gallium exposure is preferably in the range of 0.5 to 5 monolayers. It is understood that the exposure to gallium does not imply that all of the material will actually adhere to the surface. Not wishing to be bound by theory, it is believed that the gallium atoms adhere more readily at the exposed step edges of the oxide surface. Thus, subsequent growth of gallium arsenide preferentially forms along the step edges and prefer an initial alignment in a direction parallel to the step edge, thus forming predominantly single domain material. Other materials besides gallium may also be utilized in a similar fashion, such as aluminum and indium or a combination thereof.

After the deposition of the template, a compound semiconductor material such as gallium arsenide may be deposited. The arsenic source shutter is preferably opened prior to opening the shutter of the gallium source. Small amounts of other elements may also be deposited simultaneously to aid nucleation of the compound semiconductor material layer. For example, aluminum may be deposited to form AlGaAs. As noted above, layer 38, illustrated in FIG. 4, comprises a monocrystalline material that can be grown epitaxially over a monocrystalline oxide material, such as material used to form accommodating buffer layer 24. In accordance with one embodiment of the invention, layer 38 includes materials different from those used to form layer 26. For example, in a preferred embodiment, layer 38 includes AlGaAs, which is deposited as a nucleation layer at a relatively slow growth rate. For example, the growth rate of layer 38 of AlGaAs can be approximately 0.10 - 0.5 μm/hr. In this case, growth can be initiated by first depositing As on template layer 30, followed by deposition of aluminium and gallium. Deposition of the nucleation layer generally is accomplished at about 300- 600° C, and preferably 400-500° C. In accordance with one exemplary embodiment of the invention, the nucleation layer is about 1 nm to about 500 nm thick, and preferably 5nm to about 50 nm. In this case, the aluminum source shutter is preferably opened prior to opening the gallium source shutter. The amount of aluminum is preferably in the range from 0 to 50% (expressed as a percentage of the aluminum content in the AlGaAs layer), and is most preferably about 15-25%. Other materials, such as InGaAs, could also be used in a similar fashion. Once the growth of compound semiconductor material is initiated, other mixtures of compound semiconductor materials can be grown with various compositions and various thicknesses as required for various applications. For example, a thicker layer of GaAs may be grown on top of the AlGaAs layer to provide a semi-insulating buffer layer prior to the formation of device layers. The quality of the compound semiconductor material can be improved by including one or more in-situ anneals at various points during the growth. The growth is interrupted, and the substrate is raised to a temperature of between 500°- 650°C, and preferably about 550°- 600°C. The anneal time depends on the temperature selected, but for an anneal of about 550°C, the length of time is preferably about 15 minutes. The anneal can be performed at any point during the deposition of the compound semiconductor material, but preferably is performed when there is 50nm to 500nm of compound semiconductor material deposited. Additional anneals may also be done, depending on the total thickness of material being deposited.

In accordance with one embodiment, monocrystalline material layer 26 is GaAs. Layer 26 may be deposited on layer 24 at various rates, which may vary from application to application; however in a preferred embodiment, the growth rate of layer 26 is about 0.2 to 1.0 μm/hr. The temperature at which layer 26 is grown may also vary, but in one embodiment, layer 26 is grown at a temperature of about 300°- 600° C and preferably about 350°- 500° C.

Turning now to FIGS. 10-13, the formation of a device structure in accordance with still another embodiment of the invention is illustrated in cross- section. This embodiment utilizes the formation of a compliant substrate which relies on the epitaxial growth of single crystal oxides on silicon followed by the epitaxial growth of single crystal silicon overlying the oxide.

An accommodating buffer layer 74 such as a monocrystalline oxide layer is first grown on a substrate layer 72, such as silicon, with an amorphous interface layer 78 as illustrated in FIG. 10. Monocrystalline oxide layer 74 may comprise any of those materials previously discussed with reference to layer 24 in FIGS. 1, 2, and 4 while amorphous interface layer 78 is preferably comprised of any of those materials previously described with reference to the layer 28 illustrated in FIGS. 1, 2, and 4. Substrate 72, although preferably silicon, may also comprise any of those materials previously described with reference to substrate 22 in FIGS. 1-4.

Next, a silicon layer 81 is deposited over monocrystalline oxide layer 74 via MBE, CVD, MOCVD, MEE, ALE, PVD, CSD, PLD, and the like, as illustrated in FIG. 11, with a thickness of up to a few tens of nanometers but preferably with a thickness of about 5 nm. Monocrystalline oxide layer 74 preferably has a thickness of about 2 to 10 nm. Rapid thermal annealing is then conducted in the presence of a carbon source such as acetylene or methane, for example at a temperature within a range of about 800°C to 1000°C, to form capping layer 82 and amorphous silicate layer 86. Other suitable carbon sources may also be used as long as the rapid thermal annealing step functions to amorphize monocrystalline oxide layer 74 and to convert that monocrystalline layer into an amorphous silicate layer 86 and to carbonize top silicon layer 81 to form capping layer 82 which, in this example, would be a silicon carbide (SiC) layer as illustrate in FIG. 12. The formation of amorphous layer 86 is similar to the formation of layer 36 illustrated in FIG. 4 and may comprise any of those materials described with reference to layer 36 in FIG. 4, but the preferable material will be dependent upon capping layer 82 used for silicon layer 81.

Finally, a compound semiconductor layer 96, such as gallium nitride (GaN) is grown over the SiC surface by MBE, CVD, MOCVD, MEE, ALE, PVD, CSD, PLD, or the like to form a high quality compound semiconductor material for device formation as illustrated in FIG. 13. More specifically, the deposition of GaN and GaN based systems such as GalnN and AlGaN will result in the formation of dislocation nets confined at the silicon/amorphous region. The resulting nitride containing compound semiconductor material may comprise elements from groups III, rv and V of the periodic table and is defect free. Although GaN has been grown on SiC substrates in the past, this embodiment of the invention possesses a one step formation of the compliant substrate containing a SiC top surface and an amorphous layer on a Si surface. More specifically, this embodiment of the invention uses an intermediate single crystal oxide layer that is amorphized to form a silicate layer which adsorbs the strain between the layers. Moreover, unlike past use of a SiC substrate, this embodiment of the invention is not limited by wafer size which has usually been less than 50mm in diameter for prior art SiC substrates.

The monolithic integration of nitride containing semiconductor compounds containing group III-V nitrides and silicon devices can be used for high temperature and high power RF applications and optoelectronics. GaN systems have particular use in the photonic industry for blue/green and UV light sources and detectors. High brightness light emitting diodes (LEDs) and lasers may also be formed within the GaN system.

Clearly, those embodiments specifically describing structures having compound semiconductor portions and Group IV semiconductor portions are meant to illustrate embodiments of the present invention and not limit the present invention. There are a multiplicity of other combinations and other embodiments of the present invention. For example, the present invention includes structures and methods for fabricating material layers which form semiconductor structures, devices and integrated circuits including other layers such as metal and non-metal layers. More specifically, the invention includes structures and methods for forming a compliant substrate which is used in the fabrication of semiconductor structures, devices and integrated circuits and the material layers suitable for fabricating those structures, devices, and integrated circuits. By using embodiments of the present invention, it is now simpler to integrate devices that include monocrystalline layers comprising semiconductor and compound semiconductor materials, as well as other material layers that are used to form those devices, with other components that work better or are easily and/or inexpensively formed within semiconductor or compound semiconductor materials. This allows a device to be shrunk, the manufacturing costs to decrease, and yield and reliability to increase. In accordance with one embodiment of this invention, a monocrystalline semiconductor or compound semiconductor wafer can be used in forming monocrystalline material layers over the wafer. In this manner, the wafer is essentially a "handle" wafer used during the fabrication of semiconductor electrical components within a monocrystalline layer overlying the wafer. Therefore, electrical components can be formed within semiconductor materials over a wafer of at least approximately 200 millimeters in diameter and possibly at least approximately 300 millimeters.

By the use of this type of substrate, the relatively inexpensive "handle" wafer overcomes the fragile nature of wafers fabricated of monocrystalline compound semiconductor or other monocrystalline material by placing the materials over a relatively more durable and easy to fabricate base substrate. Therefore, an integrated circuit can be formed such that all electrical components, and particularly all active electronic devices, can be formed within or using the monocrystalline material layer even though the substrate itself may include a different monocrystalline semiconductor material. Fabrication costs for compound semiconductor devices and other devices employing non-silicon monocrystalline materials should decrease because larger substrates can be processed more economically and more readily compared to the relatively smaller and more fragile substrates (e.g., conventional compound semiconductor wafers).

FIG. 14 illustrates schematically, in cross section, a device structure 50 in accordance with a further embodiment of the invention. Device structure 50 includes a monocrystalline semiconductor substrate 52, preferably a monocrystalline silicon wafer. In some applications substrate 52 may also include an epitaxial silicon layer 51. Monocrystalline semiconductor substrate 52 includes two regions, 53 and 57. An electrical semiconductor component generally indicated by the dashed line 56 is formed, at least partially, in region 53. Electrical component 56 can be a resistor, a capacitor, an active semiconductor component such as a diode or a transistor or an integrated circuit such as a CMOS integrated circuit. For example, electrical semiconductor component 56 can be a CMOS integrated circuit configured to perform digital signal processing or another function for which silicon integrated circuits are well suited. The electrical semiconductor component in region 53 can be formed by conventional semiconductor processing as well known and widely practiced in the semiconductor industry. A layer of insulating material 59 such as a layer of silicon dioxide or the like may overlie electrical semiconductor component 56.

Insulating material 59 and any other layers that may have been formed or deposited during the processing of semiconductor component 56 in region 53 are removed from the surface of region 57 to provide a bare silicon surface in that region. As previously explained, bare silicon surfaces are highly reactive and a native silicon oxide layer can quickly form on the bare surface. A layer of barium or barium and oxygen is deposited onto the native oxide layer on the surface of region 57 and is reacted with the oxidized surface to reduce the native oxide and to form a first template layer (not shown). In accordance with one embodiment, a monocrystalline oxide layer 65 is formed overlying the template layer by a process of molecular beam epitaxy. Reactants including barium, titanium and oxygen are reacted on the template layer to form a monocrystalline barium titanante layer in a manner similar to that discussed in detail above. After a suitable layer of monocrystalline oxide is formed, the partial pressure of oxygen in the MBE reactor chamber is then increased to provide an overpressure of oxygen and to allow oxygen to diffuse through the growing monocrystalline oxide layer. The oxygen diffusing through the barium titanate layer reacts with silicon at the surface of region 57 to form an amorphous layer of silicon oxide 62 on second region 57 at the interface between silicon substrate 52 and monocrystalline oxide layer 65. Layers 65 and 62 may be subject to an annealing process as described above in connection with FIG. 4 to form a single amorphous accommodating layer.

In accordance with an embodiment of the invention, the step of depositing monocrystalline oxide layer 65 is terminated by depositing a second template layer 64, which can be 0.5-10 monolayers of titanium, barium, barium and oxygen, or titanium and oxygen. A layer 66 of a monocrystalline compound semiconductor material is then deposited overlying second template layer 64 by a process of molecular beam epitaxy in a manner similar to that described in detail above. The deposition of layer 66 is initiated by depositing a layer of arsenic onto template 64. This initial step is followed by depositing gallium and arsenic to form monocrystalline gallium arsenide 66. Alternatively, strontium can be substituted for barium in the above example.

In accordance with a further embodiment, a semiconductor component, generally indicated by a dashed line 68, is formed in compound semiconductor layer 66. Semiconductor component 68 can be formed by processing steps conventionally used in the fabrication of gallium arsenide or other III-V compound semiconductor material devices. Semiconductor component 68 can be any active or passive component, and preferably is a semiconductor laser, light emitting diode, photodetector, he teroj unction bipolar transistor (HBT), high frequency MESFET, or other component that utilizes and takes advantage of the physical properties of compound semiconductor materials. A metallic conductor schematically indicated by the line 70 can be formed to electrically couple device 68 and device 56, thus implementing an integrated device that includes at least one component formed in silicon substrate 52 and one device formed in monocrystalline compound semiconductor material layer 66. Although illustrative structure 50 has been described as a structure formed on a silicon substrate 52 and having a barium (or strontium) titanate layer 65 and a gallium arsenide layer 66, similar devices can be fabricated using other substrates, other monocrystalline oxide layers and other compound semiconductor layers as described elsewhere in this disclosure.

Clearly, those embodiments specifically describing structures having compound semiconductor portions and Group IV semiconductor portions, are meant to illustrate embodiments of the present invention and not to limit the present invention. There are a multiplicity of other combinations and other embodiments of the present invention. For example, the present invention includes structures and methods for fabricating material layers which form semiconductor structures, devices and integrated circuits including other layers such as metal and non-metal layers. More specifically, the invention includes structures and methods for forming a compliant substrate which is used in the fabrication of semiconductor structures, devices and integrated circuits and the material layers suitable for fabricating those structures, devices, and integrated circuits. By using embodiments of the present invention, it is now simpler to integrate devices that include monocrystalline layers comprising semiconductor and compound semiconductor materials as well as other material layers that are used to form those devices with other components that work better or are easily and/or inexpensively formed within semiconductor or compound semiconductor materials. This allows the size of a device to be reduced, the manufacturing costs to decrease, and yield and reliability to increase.

In the foregoing specification, the invention has been described with reference to specific embodiments. However, one of ordinary skill in the art appreciates that various modifications and changes can be made without departing from the scope of the present invention as set forth in the claims below. Accordingly, the specification and figures are to be regarded in an illustrative rather than a restrictive sense, and all such modifications and changes are intended to be included within the scope of the present invention.

Benefits, other advantages, and solutions to problems have been described above with regard to specific embodiments. However, the benefits, advantages, solutions to problems, and any element(s) that may cause any benefit, advantage, or solution to occur or become more pronounced are not to be construed as a critical, required, or essential features or elements of any or all the claims. As used herein, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.

Claims

We Claim:

1. A method for growing a monocrystalline oxide layer on a monocrystalline substrate comprising the steps of: positioning a monocrystalline substrate having a surface within a reaction chamber; removing any oxide that may be present on the surface of the substrate; heating the substrate to a first temperature; introducing oxygen to the reaction chamber to establish a first partial pressure of oxygen in the reaction chamber, where the chosen combination of said first temperature and said first partial pressure is such that the substrate will not substantially react with the oxygen; introducing at least one reactant to the reaction chamber and reacting the at least one reactant and the oxygen to form a first layer of oxide; stopping the introduction of said at least one reactant to the reaction chamber; reducing the partial pressure of oxygen in the reaction chamber to a second partial pressure of oxygen less than the first partial pressure of oxygen; and heating the substrate to a second temperature greater than the first temperature, where the second temperature is high enough to improve the crystalline quality of the first layer, and the second temperature is not so high as to cause the substrate to react with the first layer.

2. The method of claim 1 further comprising the steps of: after the step of heating the substrate to a second temperature, lowering the temperature of the substrate to a third temperature less than the second temperature; introducing oxygen to the reaction chamber to establish a third partial pressure of oxygen in the reaction chamber, the third partial pressure of oxygen equal to or greater than the second partial pressure of oxygen; again introducing at least one reactant to the reaction chamber and reacting the at least one reactant and the oxygen to form a second layer of oxide overlying the first layer; stopping the step of again introducing said at least one reactant to the reaction chamber; reducing the partial pressure of oxygen in the reaction chamber to a fourth partial pressure of oxygen less than or equal to the third partial pressure of oxygen; and heating the substrate to a fourth temperature greater than the third temperature, where the fourth temperature is high enough to improve the crystalline quality of the second layer.

3. The method of claim 2 further comprising the step of forming a template overlying the second layer.

4. The method of claim 3 further comprising the step of forming a third monocrystalline layer overlying the second layer.

5. The method of claim 4 wherein the step of forming a third monocrystalline layer comprises the step of forming a monocrystalline layer of semiconductor material, compound semiconductor material, oxide material, metal or non-metal material.

6. The method of claim 2 further comprising the step of forming a layer of gate electrode material overlying the second layer.

7. The method of claim 1 wherein the monocrystalline substrate is a monocrystalline silicon substrate.

8. The method of claim 7 further comprising the step of; after the step of heating the substrate to a second temperature, heating the substrate in an oxygen ambient to form an amorphous layer of silicon oxide between the monocrystalline silicon substrate and the first layer.

9. The method of claim 7 wherein the step of introducing at least one reactant comprises the step of introducing constituent elements of perovskite oxides.

10. The method of claim 7 wherein the step of introducing at least one reactant comprises the step of introducing an alkaline earth metal and a transition metal to the reaction chamber.

11. The method of claim 10 wherein the step of introducing at least one reactant comprises the step of introducing strontium and titanium to the reaction chamber.

12. The method of claim 1 wherein the step of removing any oxide comprises the step of depositing an alkaline earth metal overlying the any oxide and reacting the alkaline earth metal with the any oxide to reduce the any oxide.

13. The method of claim 12 further comprising the step of depositing additional alkaline earth metal onto the surface of the monocrystalline substrate after the step of reacting.

14. The method of claim 1 further comprising the step of monitoring the first layer of oxide using RHEED during the step of heating the substrate to a second temperature.

15. The method of claim 14 wherein the step of heating the substrate to a first temperature comprises the step of heating the substrate to a temperature less than 400°C.

16. The method of claim 15 wherein the step of heating the substrate to a first temperature comprises the step of heating the substrate to a temperature of about 300°C.

17. The method of claim 15 wherein the step of heating the substrate to a second temperature comprises the step of heating the substrate to a temperature between

500°C and 750°C.

18. The method of claim 17 where the first layer has a thickness of about 1-15 angstroms.

19. The method of claim 1 further comprising the step of forming a second monocrystalline layer overlying the first layer.

20. The method of claim 19 wherein the step of forming a second monocrystalline layer comprises the step of forming a monocrystalline layer of material selected from the group consisting of semiconductor material, compound semiconductor material, oxide material, metal and non-metal material.

21. The method of claim 1 further comprising the step of forming a layer of gate electrode material overlying the first layer.

22. A method for fabricating a semiconductor structure comprising the steps of: positioning an oxidizable monocrystalline substrate having a surface within a reaction chamber; removing any oxide that may be present on the surface of the substrate; heating the substrate to a first temperature; introducing oxygen to the reaction chamber to establish a partial pressure of oxygen in the reaction chamber; introducing at least one reactant to the reaction chamber; reacting the oxygen and the at least one reactant at the surface of the substrate to grow an oxide on the surface; decreasing the partial pressure of oxygen in the reaction chamber; terminating the step of introducing a metal reactant; and heating the substrate to a second temperature greater than the first temperature to improve the crystalline quality of the oxide; wherein the first temperature is a temperature at which oxidation of the at least one reactant is kinetically favored in comparison to oxidation of the oxidizable substrate.

23. A process for fabricating a semiconductor structure comprising: providing a monocrystalline silicon substrate; and depositing a monocrystalline perovskite oxide film overlying the monocrystalline silicon substrate, the step of depositing comprising the steps of: placing the substrate in a reactor chamber; removing any oxide that may be present on the surface of the substrate; heating the substrate to a temperature less than about 400°C; introducing oxygen and a plurality of metal reactants to the reactor chamber to grow about 1-15 angstroms of a first layer of perovskite oxide on the substrate; and heating the substrate to a second temperature between about 500°C and about 750°C to improve the crystalline quality of the perovskite oxide.

24. The process of claim 23 with the additional step of forming a second layer overlying the monocrystalline perovskite oxide film.

25. The process of claim 24 wherein the step of forming a second layer comprises the step of epitaxially forming a monocrystalline layer of material selected from the group consisting of semiconductor material, compound semiconductor material, oxide material, metal and non-metal material.

26. The process of claim 23 further comprising the step of forming a template layer on the monocrystalline perovskite oxide film before the step of epitaxially forming a monocrystalline second layer.

27. The process of claim 26 wherein the step of forming a template layer comprising the step of forming a template layer comprising a wetting layer.