Abstract:
A three-dimensional polycrystalline semiconductor material provides a major ingredient forming individual crystalline grains having a nominal maximum grain diameter less than or equal to 50 nm, and a minor ingredient forming boundaries between the individual crystalline grains.

Description:
CROSS REFERENCE TO RELATED APPLICATIONS 
       [0001]    This application claims priority from U.S. provisional application 61/409,846 entitled “QUANTUM DOT FIELD EFFECT TRANSISTOR IN A FULLY INTEGRATED SILICON CARRIER AND METHOD OF MANUFACTURE” filed Nov. 3, 2010. 
     
    
     FIELD OF THE INVENTION 
       [0002]    The present invention relates generally to bulk semiconducting materials that are structurally designed and chemically engineered at nanometer dimensional scales to exhibit properties of a three-dimensional electron gas, and in particular to the incorporation of these unique semiconductor materials into a semiconductor carrier that is used to electrically interconnect additional semiconductor die comprising a larger microelectronic system with other active electrical or opto-electronic devices monolithically integrated into the carrier surface. 
       BACKGROUND OF THE INVENTION 
       [0003]    The present invention relates specifically to a bulk semiconducting material that consists of a uniform distribution of nanoscale polycrystalline grains wherein the diameter of the polycrystalline grains is limited to nanometer physical dimensions such that the nanoscale texture of the semiconducting material induces quantum-size effects within the polycrystalline grains that endow the bulk semiconductor with electrical or optical properties (herein referred to as “general dielectric properties”) of a three-dimensional (3D) electron gas. An additional specific embodiment of the invention relates to methods and processes that diffuse electrically conducting or electrical insulating materials into the grain boundaries of the nanoscale polycrystalline grains. 
         [0004]    The present invention relates generally to the monolithic assembly of an active electronic, photonic, or opto-electronic device that comprises a layer of semiconductor material having thickness greater than 50 nm which exhibits the general dielectric properties of a 3D electron gas onto a semiconductor chip carrier that is used to electrically interconnect various additional semiconductor die into a more sophisticated microelectronic system. Such various active electronic or opto-electronic devices may include, but are not limited to, high power density/high-speed power management circuits, stable clock generators, electrical signal modulators, optical sensors, optical power generators, optical signal generators and/or modulators or thermoelectric systems, 
       1. DESCRIPTION OF THE PRIOR ART 
       [0005]    T. J. Phillips et al. (U.S. Pat. No. 7,173,292), (hereinafter referred to as Phillips &#39;292), teaches that runaway currents (avalanche breakdown) caused by impact ionization in modulation-doped field effect (MODFET) or high electron mobility (HEMT) transistors applied to narrow band gap semiconductor materials is mitigated or substantially eliminated by forming a quantum well field effect transistor (QWFET). The quantum well FET consists of thin multi-layered structures comprising one or more wide band gap semiconductors. (See  FIGS. 1&amp;2 ).  FIG. 1  depicts a vertical cross section of a QWFET  1  that comprises a quantum well region  2  embedded between two wide band gap semiconductor layers  3 , 4 . The quantum well region  2  consists of a plurality of differing semiconductor layers  5 , 6 , 7 . The central layer  6  forms a primary conduction channel that is bounded by semiconductor materials  5 , 7  forming secondary conduction channels having semiconductor band gaps  21 , 22  greater than the band gap  23  of semiconductor material that is used in the layer forming the primary conduction channel  6 , but less than the band gaps  24 , 25  of the wide band gap semiconductor layers  3 , 4 .  FIG. 2  shows the representative energy band gap diagram  20  for the layered semiconductor structure depicted in  FIG. 1  viewed from cross-sectional perspective defined by X-X′. 
         [0006]    The field effect device is created by inserting the quantum well region  2  between two conductive doped source  8  and drain  9  regions. An electrical bias applied to the gate electrode  10  is then used to modulate current supplied to the source electrode  11  when it is collected by the drain electrode  12 . The high charged carrier mobilities available in QWFET devices enable high switching speeds reported in the range between 250 GHz to 1 THz, and thus have value in high switching speed systems or millimeter-wave communications systems. 
         [0007]    In a QWFET device, the central layer  6  must be sufficiently thin (20-50 nm) to form a 2-D electron gas through quantization effects in the quantum well contained in the primary conduction channel. The quantization effects are generated by the nanometer scale thickness of the central layer  6  and the height of the band edges  26 , 27  created by contacting to the semiconductor layers  5 , 7  that form the quantum well  28 . These quantization effects create the discrete energy levels  29 , 30  of the high electron mobility  2 -electron gas. The semiconductor layers  5 , 7  provide higher ionization thresholds that prevent currents flowing in the primary conduction channel in the central layer  6  from undergoing avalanche breakdown through impact ionization processes. Examples of low band gap semiconductor materials used in the primary channels are indium antimonide (InSb), indium arsenide (InAs), indium arsenic antimonide (InAs (1-y) Sb y ), indium gallium antimonide (In (1-x) Ga x Sb), and/or indium gallium arsenide (In (1-x) Ga x As). 
       2. DEFINITION OF TERMS 
       [0008]    The term “active component” is herein understood to refer to its conventional definition as an element of an electrical circuit that that does require electrical power to operate and is capable of producing power gain. 
         [0009]    The term “alkali metal” is herein understood to refer to its conventional definition meaning the group of metallic elements in column IA of the periodic table, consisting of lithium, sodium, potassium, rubidium, cesium, and francium. 
         [0010]    The term “alkaline earth metal” is herein understood to refer to its conventional definition meaning the group of metallic elements found in column IIA of the periodic table, consisting of magnesium, calcium, strontium, barium, and radium. 
         [0011]    The term “amorphous material” is herein understood to mean a material that does not comprise a periodic lattice of atomic elements, or lacks mid-range (over distances of 10&#39;s of nanometers) to long-range crystalline order (over distances of 100&#39;s of nanometers). 
         [0012]    The terms “chemical complexity”, “compositional complexity”, “chemically complex”, or “compositionally complex” are herein understood to refer to a material, such as a metal or superalloy, compound semiconductor, or ceramic that consists of three (3) or more elements from the periodic table. 
         [0013]    The term “chip carrier” is herein understood to refer to an interconnect structure built into a semiconductor substrate that contains wiring elements and embedded active components that route electrical signals between one or more integrated circuits mounted on chip carrier&#39;s surface and a larger electrical system that they may be connected to. 
         [0014]    The term “electron gas” is herein understood to refer to its generally accepted definition as a collection of electrons (or holes) that are free to move within a modified solid via tunneling processes and have higher mobilities than they would normally have in a similar unmodified solid, wherein quantization effects generated by the solid&#39;s modification (typically nanoscale layering) induce a quantum energy well that govern and define the transport properties of the electrons (holes) and minimize interactions between the electron (holes) located within the quantum energy well. 
         [0015]    The term “FET” is herein understood to refer to its generally accepted definition of a field effect transistor wherein a voltage applied to an insulated gate electrode induces an electrical field through insulator that is used to modulate a current between a source electrode and a drain electrode. 
         [0016]    The term “halogen” is herein understood to refer to its conventional definition meaning the nonmetallic elements contained in column VIIA of the periodic table consisting of fluorine, chlorine, bromine, iodine, and astatine. 
         [0017]    The term “halogenated” is herein understood to refer to its conventional definition meaning a molecule or substance that has been treated or combined with a halogen. 
         [0018]    The term “integrated circuit” is herein understood to mean a semiconductor chip into which a large, very large, or ultra-large number of transistor elements have been embedded. 
         [0019]    The term “LCD” is herein understood to mean a method that uses liquid precursor solutions to fabricate materials of arbitrary compositional or chemical complexity as an amorphous laminate or free-standing body or as a crystalline laminate or free-standing body that has atomic-scale chemical uniformity and a microstructure that is controllable down to nanoscale dimensions. 
         [0020]    The term “liquid precursor solution” is herein understood to mean a solution of hydrocarbon molecules that also contains soluble metalorganic compounds that may or may not be organic acid salts of the hydrocarbon molecules into which they are dissolved. 
         [0021]    The term “microstructure” is herein understood to define the elemental composition and physical size of crystalline grains forming a material substance. 
         [0022]    The term “mismatched materials” is herein understood to define two materials that have dissimilar crystalline lattice structure, or lattice constants that differ by 5% or more, and/or thermal coefficients of expansion that differ by 10% or more. 
         [0023]    The term “nanoscale” is herein understood to define physical dimensions measured in lengths ranging from 1 nanometer (nm) to 100&#39;s of nanometers (nm). 
         [0024]    The term “opto-electronic device” is herein understood to refer to any device that uses an electrical signal to modulate an optical signal having energetic characteristics defined by the optical, infrared (near, mid or far), millimeter wave, sub-millimeter wave, or ultraviolet (near or far) regions of the electromagnetic spectrum, or visa-versa. 
         [0025]    The term “passive component” is herein understood to refer to its conventional definition as an element of an electrical circuit that that does not require electrical power to operate and is capable of altering an electrical signal&#39;s amplitude and/or phase or being used as an energy storage device. 
         [0026]    The term “photonic device” is herein understood to refer to a device that uses a signal having energetic characteristics defined by the optical, infrared (near, mid, or far), millimeter wave, sub-millimeter wave, or ultraviolet (near or far) electromagnetic spectrum to modulate one or more additional signal having energetic characteristics defined by the optical, infrared (near, mid, or far), millimeter wave, sub-millimeter wave or ultraviolet (near or far) regions of the electromagnetic spectrum. 
         [0027]    The term “power FET” is herein understood to refer to the generally accepted definition for a large signal vertically configured MOSFET and covers multi-channel (MUCHFET), V-groove MOSFET, truncated V-groove MOSFET, double-diffusion DMOSFET, modulation-doped transistors (MODFET), heterojunction transistors (HETFET), and insulated-gate bipolar transistors (IGBT). 
         [0028]    The term “quantum dot” is herein understood to apply to its conventional meaning of a material domain that is small enough to induce quantum-size effects that exhibit the electronic, optical, or opto-electronic characteristics of an electron gas. 
         [0029]    The term “standard operating temperatures” is herein understood to mean the range of temperatures between −40° C. and +125° C. 
         [0030]    The terms “tight tolerance” or “critical tolerance” are herein understood to mean a performance value, such as a capacitance, inductance, or resistance that varies less than ±1% over standard operating temperatures. 
         [0031]    The term “II-VI compound semiconductor” is herein understood to refer to its conventional meaning describing a compound semiconductor comprising at least one element from column IIB of the periodic table consisting of: zinc (Zn), cadmium (Cd), or mercury (Hg); and, at least one element from column VI of the periodic table consisting of: oxygen (O), sulfur (S), selenium (Se), or tellurium (Te). 
         [0032]    The term “III-V compound semiconductor” is herein understood to refer to its conventional meaning describing a compound semiconductor comprising at least one semi-metallic element from column III of the periodic table consisting of: boron (B), aluminum (Al), gallium (Ga), and indium (In); and, at least one gaseous or semi-metallic element from the column V of the periodic table consisting of: nitrogen (N), phosphorous (P), arsenic (As), antimony (Sb), or bismuth (Bi). 
         [0033]    The term “IV-IV compound semiconductor” is herein understood to refer to its conventional meaning describing a compound semiconductor comprising a plurality of elements from column IV of the periodic table consisting of: carbon (C), silicon (Si), germanium (Ge), tin (Sn), or lead (Pb). 
         [0034]    The term “IV-VI compound semiconductor” is herein understood to refer to its conventional meaning describing a compound semiconductor comprising at least one element from column IV of the periodic table consisting of: carbon (C), silicon (Si), germanium (Ge), tin (Sn), or lead (Pb); and, at least one element from column VI of the periodic table consisting of: sulfur (S), selenium (Se), or tellurium (Te). 
       SUMMARY OF THE INVENTION 
       [0035]    The present invention generally relates to fully integrated semiconductor chip carriers that contain systems that function at high switching speeds, and in particular to processes and methods that enable the monolithic integration of active devices comprising a bulk material layer exhibiting quantum-size effects or the characteristics of a quantum dot throughout the bulk material layer. 
         [0036]    One embodiment of the present invention provides a three-dimensional polycrystalline semiconductor material, comprising a major ingredient forming individual crystalline grains having a nominal maximum grain diameter less than or equal to 50 nm, and a minor ingredient forming boundaries between the individual crystalline grains. 
         [0037]    The minor ingredient may surround the crystalline grains of the major ingredient. Quantum size effects within the polycrystalline material may induce a free electron gas characteristic of a quantum well. The polycrystalline material may form a three-dimensional quantum well structure. The molar concentrations of the minor ingredient may be between 0.0001 mol % and 0.75 mol % of the polycrystalline material. The major ingredient may comprise the crystalline grains is silicon, germanium, tin, or any admixture thereof. The minor ingredient forming the grain boundaries may be an insulating, semi-insulating, or semiconducting material consisting of a metal halide comprising an alkali element from the first (I) column or an alkaline earth element from second (II) column of the periodic table, or a transition-metal having chemical properties similar to an alkali or alkaline earth metal, and a halogen element selected from the seventh (VII) column of the periodic table. The insulating or semi-insulating material has an energy band gap may be larger than the band gap of the semiconductor material comprising the polycrystalline grain. The minor ingredient forming the grain boundaries may be a conductive material consisting of an alkali element from the first (I) column or an alkaline earth element from second (II) column of the periodic table, or a transition-metal having chemical properties similar to an alkali or alkaline earth metal. The major ingredient may comprise crystalline grains is a III-V compound semiconducting material and the minor ingredient forming the boundaries may be an insulating, semi-insulating, or semiconducting material consisting of a metal halide comprising an alkali element from the first (I) column or a transition-metal having chemical properties similar to an alkali metal, and a halogen element selected from the seventh (VII) column of the periodic table. The major ingredient of the crystalline grains may be a II-VI compound semiconductor and the minor ingredient forming the boundaries is silicon, silicon carbide, germanium, tin or an admixture thereof. The polycrystalline material may have a three dimensional size that is greater than 50 nm in every direction. The polycrystalline material may be monolithically integrated into an active device. The active device may be a field effect transistor, an opto-electronic device or a photonic device. The major ingredient comprising crystalline grains may be a III-V compound semiconducting material and the minor ingredient forming the boundaries may be a conducting material consisting of an alkali element from the first (I) column or a transition-metal having chemical properties similar to an alkali metal. 
         [0038]    Another embodiment of the present invention provides a semiconductor carrier, comprising an active device including a semiconductor layer that is monolithically integrated into the semiconductor carrier and is comprised of a nanoscale polycrystalline assembly including semiconducting crystalline grains having maximal physical dimensions in the range of 20 nm to 50 nm that are enveloped by a grain boundary material that is 2 nm to 10 nm thick, such that the quantum size effects within the polycrystalline grain induce a free electron gas characteristic of a quantum well. 
         [0039]    The active device may be a field effect transistor, an opto-electronic device or a photonic device. The active device may comprise a power management module monolithically integrated on to its surface. The active device may comprise a semiconductor die. The semiconductor carrier may have active circuitry embedded within the carrier substrate. 
         [0040]    Yet another embodiment of the present invention provides a method of fabricating a semiconductor layer comprised of a nanoscale polycrystalline assembly including semiconducting crystalline grains having maximal physical dimensions in the range of 20 nm to 50 nm that are enveloped by a grain boundary material that is 2 nm to 10 nm thick, such that the quantum size effects within the polycrystalline grain induce a free electron gas characteristic of a quantum well, comprising the steps of: forming a solution of low volatility liquid metalorganic precursors having stoichiometric ratios suitable for producing majority phase polycrystalline grains consisting of an elemental semiconductor or a desired compound semiconductor stoichiometry; adding to said solution dopants in concentrations in the range of 0.0001 mol % to 0.5 mol % having stoichiometric ratios suitable for producing an insulating, semi-insulating, or semiconducting secondary phase material in the grain boundary of the majority phase polycrystalline grains; adding to said solution precursors for the dopants to the majority phase polycrystalline grains in the concentrations desired within the polycrystalline grains, heating a substrate upon which the semiconductor layer will be formed a temperature in the range of 250° C. to 500° C.; simultaneously decomposing the non-volatile metalorganic precursors on the substrate in an inert or reducing gas atmosphere to form an amorphous deposit having stoichiometric precision that is chemically uniform at the atomic scale; baking said amorphous deposit to remove organic residue from the deposit; annealing said baked deposit for a minimum of 5 seconds in ionized argon plasma using an applied power of 50 W to 300 W at a substrate temperature between 40° C. and 400° C. and a pressure in the range of 1,500 mTorr to 5,000 mTorr; and optionally adding nitrogen, and/or reducing partial pressure ratios of carbon dioxide and carbon monoxide to the ionized argon plasma. 
         [0041]    The semiconducting material of the crystalline grains may be silicon, germanium, tin, or any admixture thereof. The grain boundary material may be an insulating, semi-insulating, or semiconducting material consisting of a metal halide comprising an alkali element from the first (I) column or an alkaline earth element from second (II) column of the periodic table, or a transition-metal having chemical properties similar to an alkali or alkaline earth metal, and a halogen element selected from the seventh (VII) column of the periodic table. The insulating or semi-insulating material may have an energy band gap that is larger than the band gap of the semiconductor material comprising the polycrystalline grain. The semiconductor material of the crystalline grains may be a III-V compound semiconducting material and the grain boundary material is an insulating, semi-insulating, or semiconducting material consisting of a metal halide comprising an alkali element from the first (I) column or a transition-metal having chemical properties similar to an alkali metal, and a halogen element selected from the seventh (VII) column of the periodic table. The semiconducting crystalline grains may be a II-VI compound semiconductor and the grain boundary material may be silicon, silicon carbide, germanium, tin or an admixture thereof. 
     
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         [0042]    The present invention is illustratively shown and described in reference to the accompanying drawings, in which: 
           [0043]      FIG. 1  depicts the physical structure of a prior art quantum well field effect transistor. 
           [0044]      FIG. 2  depicts the energy band diagram of the quantum well device of  FIG. 1 . 
           [0045]      FIG. 3  depicts a fully integrated silicon chip carrier. 
           [0046]      FIG. 4  is a table listing charged carrier mobilities in various elemental and compound semiconductors. 
           [0047]      FIG. 5A  depicts a polycrystalline semiconductor containing nanoscale grains that have metallic elements lodged within the grain boundaries. 
           [0048]      FIG. 5B  depicts a polycrystalline semiconductor containing nanoscale grains that have insulating compounds lodged within the grain boundaries. 
           [0049]      FIG. 6A  depicts a two-dimensional (2-D) image of the energy band structure of a three-dimensional (3-D) quantum-dot semiconductor layer formed within a polycrystalline semiconductor matrix comprised of nanoscale grains that have metallic elements lodged within the grain boundaries. 
           [0050]      FIG. 6B  depicts a two-dimensional (2-D) image of the energy band structure of a three-dimensional (3-D) quantum-dot semiconductor layer formed within a polycrystalline semiconductor matrix comprised of nanoscale grains that have insulating compounds lodged within the grain boundaries. 
           [0051]      FIG. 7  provides a cross-sectional view of a quantum dot field effect transistor. 
           [0052]    FIGS.  8 A, 8 B, 8 C are cross-sectional substrate views used to depict the method for making the semiconductor layer of a quantum well field effect transistor using a halogenated metalorganic precursor compound. 
           [0053]      FIG. 8D  is a chemical diagram of a metalorganic precursor compound that can be used in association with  FIGS. 8A-8C . 
           [0054]      FIG. 9  depicts an IGBT power FET that contains a nanoscale polycrystalline 3D electron gas layer. 
           [0055]      FIG. 10  depicts a semiconductor carrier comprising a quantum-dot opto-electronic or photonic device monolithically integrated onto its surface. 
           [0056]      FIG. 11  is a Table I showing Representative Grain-Grain Boundary Combinations for Insulating/Semi-insulating/Semiconducting Grain Boundaries for certain materials. 
           [0057]      FIG. 12  is a Table II showing Representative Grain-Grain Boundary Combinations for Insulating/Semi-insulating/Semiconducting Grain Boundaries for certain materials. 
       
    
    
     DESCRIPTION OF THE PREFERRED EMBODIMENT 
       [0058]    This application is copending with de Rochemont U.S. Ser. No. 13/168,922, entitled “SEMICONDUCTOR CARRIER WITH VERTICAL FET POWER MODULE”, filed Jun. 24, 2011 (de Rochemont &#39;922), and de Rochemont U.S. Ser. No. 13/163,654, entitled “FREQUENCY-SELECTIVE DIPOLE ANTENNA”, filed Jun. 17, 2011 (de Rochemont &#39;654), which are incorporated herein by reference. The current application instructs means to insert a bulk semiconductor layer into an active component integrated on a semiconductor carrier, where the bulk semiconductor layer has thickness greater than 50 nm and exhibits general dielectric properties of an electron gas. One counterpart application (de Rochemont &#39;922) instructs means to fully integrate a high efficiency, power management system as a monolithic structure on a semiconductor carrier to modulate high current levels using a resonant three-dimensional gate structure enabled by serpentine windings. The other counterpart application, (de Rochemont &#39;654), instructs methods to form a conducting element as a serpentine winding by folding the conducting element in ways that introduce localized regions of capacitive or inductive loading, such that the combination of localized reactive loads along the length of the folded conductor form a distributed network filter. It goes on to illustrate how two mirror image serpentine elements so formed function as a dipole antenna that is resonant over selective frequencies. The counterpart application de Rochemont &#39;654 also instructs the insertion of tight-tolerance electroceramic material within the regions of localized reactive loading to increase or more precisely tune the coupling strength of localized reactive loads. The current application is also filed jointly with de Rochemont U.S. Ser. No. 13/216,692, entitled “POWER FET WITH RESONANT TRANSISTOR GATE”, filed Aug. 23, 2011 (de Rochemont &#39;692), which is incorporated herein by reference. The co-pending application de Rochemont &#39;692 instructs a power management module that modulates large currents at low current densities at pre-determined frequencies and methods to form the power management module on a semiconductor carrier. 
         [0059]    The current application incorporates by reference all matter contained in de Rochemont, U.S. Ser. No. 11/479,159, filed Jun. 30, 2006, entitled “ELECTRICAL COMPONENT AND METHOD OF MANUFACTURE” (the &#39;159 application), de Rochemont, U.S. Ser. No. 11/620,042 filed Jan. 6, 2007 entitled “POWER MANAGEMENT MODULES” (the &#39;042 application), de Rochemont and Kovacs, U.S. Ser. No. 12/843,112 filed Jul. 26, 2010, “LIQUID CHEMICAL DEPOSITION PROCESS APPARATUS AND EMBODIMENTS”, (the &#39;112 application), de Rochemont U.S. Ser. No. 13/152,222, entitled “MONOLITHIC DC/DC POWER MANAGEMENT MODULE WITH SURFACE FET”, filed Jun. 2, 2011 (the &#39;222 application), and de Rochemont, U.S. Ser. No. 13/182,405, entitled “CUTTING TOOL AND METHODS OF MANUFACTURE”, filed Jul. 13, 2011 (the &#39;405 application). The &#39;159 application discloses how LCD methods fabricate a monolithic integrated circuit comprising tight tolerance passive networks. The &#39;042 application discloses how liquid chemical deposition (“LCD”) methods fabricate a monolithic integrated power management module that includes a tunable inductor coil. The &#39;112 application discloses preferred apparatus used in applying LCD methods. The &#39;222 application instructs the monolithic integration of a low-loss power management circuit containing a surface FET. The &#39;405 application discloses LCD methods to fabricate carbide, nitride and MAX-phase materials, such as silicon carbide, or complex chemistries that incorporate silicon and carbon elements. 
         [0060]    Reference is now made to  FIGS. 3-10  to better illustrate the significance of this invention.  FIG. 3  depicts a semiconductor chip carrier  100 . The present invention may be applied to high-speed computing modules, RF radio modules, fully integrated radar modules, photonic modules, and opto-electronic modules. It may also apply to any circuit containing such a module or combination of the aforementioned modules that requires high power densities and high switching speed circuitry. As depicted herein, the semiconductor chip carrier  100  contains a plurality of integrated circuits (semiconductor chips)  102 A,  102 B,  102 C,  102 D mounted either in discrete or stacked configuration on the carrier substrate  103 . The carrier substrate  103  is a larger semiconductor chip that has electrically conductive traces on its surface that are used to interconnect various components mounted or integrated thereupon. Additional low-level active circuitry, (not shown for clarity), may be embedded within the carrier substrate  103 . Such low-level active circuitry may include, but need not be limited to, latching, sensing, switching and signal drift circuitry useful in bus management systems. LCD processes may be used to integrate additional circuitry on the surface of the carrier substrate  103 , that may include, but need not be limited to, critical tolerance inductor coils  104 A,  104 B are used to form a tight tolerance LC circuit that stabilizes or actively tunes circuit clocking speeds, and/or passive networks  106  that are monolithically formed on the surface of the carrier substrate  103 . 
         [0061]    It is anticipated that the integrated circuit semiconductor die  102  will have power demand requirements in excess of 750 W-inch 2  as semiconductor manufacturing tolerances progress beyond the 22 nm line feature node. High-efficiency, high-speed fully integrated power management modules  108  are monolithically formed on the chip carrier  100 , using methods and embodiments detailed in the &#39;042, &#39;122, &#39;159, &#39;222, &#39;654, &#39;692, &#39;922 applications incorporated herein by reference. These methods and embodiments may be used to optimize data transfer between memory devices and processor die, or other semiconductor die co-located on the semiconductor carrier  100 . 
         [0062]    Reference is now made to FIGS.  4 - 8 A, 8 B, 8 C, 8 D to describe how unique attributes of LCD manufacturing methods are applied to integrate semiconductor layers having thicknesses greater than 20-50 nm that are endowed with nanoscale microstructures necessary to generate three-dimensional (3D) electron gases within a semiconductor layer. As disclosed in the above referenced applications, LCD manufacturing methods allow dissimilar and “mismatched” materials with atomic-scale chemical uniformity and stoichiometric precision to be integrated in selected areas on the surface of semiconductor substrate with surface adhesion that is stronger than the tensile strength of the deposited material. Unlike conventional material deposition techniques, LCD places no restriction on the number of elemental (chemical) components that can be incorporated with high compositional precision into the deposited material, which enables materials having high chemical complexity to be integrated into a monolithic structure. The low process temperatures (≦400° C.) used by LCD do not alter dopant profiles of active components buried within the semiconductor substrate. These low deposition temperatures allow the LCD deposit to initially form as a uniform solid solution. This, in turn, provides means to form microstructures in LCD deposits that are restricted to nanoscale dimensions by the subsequent application of rapid thermal annealing processes. Uniform chemical distribution and nanoscale microstructures (crystalline grain size) are a necessary condition to integrate electroceramic passive components having functional properties that remain stable with varying temperature, which satisfies critical performance tolerances needed to make the monolithic integration of passive circuitry within system-in-package (SiP) or a system-on-chip (SoC) economically viable. These unique attributes also enable the nanoscale modification of polycrystalline semiconductor materials that comprise a uniform assembly of granular quantum wells needed to form a 3D electron quantum gas. 
         [0063]      FIG. 4  presents a table listing the charged carrier (electron-hole) mobilities of various semiconductors that can be used by the present invention. Higher switching speeds are enabled in semiconductor systems that have higher charged carrier mobility. As instructed by the prior art (see  FIGS. 1 &amp; 2 ), ultra-high speed field effect transistors (FETs) are constructed using high charged carrier mobility semiconductor materials. These semiconductor materials typically have low effective electron mass, large ballistic mean free path and high saturation velocities. Preferred high carrier mobility semiconductor materials, such as indium antimonide (InSb), typically have low band gap energies, which makes them prone to avalanche breakdown generated by impact ionization. Since the impact ionization threshold essentially corresponds to the material band gap, the electric fields generated from relatively low source-drain voltages (V DS ) will give rise to avalanche breakdown and runaway currents that risk linear response and thermal runaway. Avalanche breakdown prevents high-speed FETs from being used in applications requiring relatively high operational voltages, such as modulators, amplifiers or FET-based logic devices, it also restricts high frequency gain values. These constraints inhibit application in systems where high power frequency signal amplification or management is desirable, such as high-speed computing or mobile communications platforms. Electron gases formed within quantum wells can further reduce effective electron mass and minimize avalanche breakdown in low band gap semiconductors. 
         [0064]    The prior art of  FIGS. 1 &amp; 2  instructs that runaway currents can be curtailed in low band gap semiconductors by forming a planar quantum well  28  by sandwiching the high carrier mobility/low band gap energy semiconductor as an ultra-thin layer  6  (20-50 nm thick) between layers  5 , 7  of a wider band gap semiconductor material, which in turn are sandwiched by layers  3 , 4  of an even wider band gap semiconductor. The narrow thickness of the ultra-thin layer  6  induces quantization effects within the quantum well  28  confined by energy band edges  26 , 27 . These quantization effects produce a 2D-electron gas having high electron mobility within the primary conduction channel defined by the quantum well  28 . The adjacent layers  5 , 7  comprising wider band gap semiconductor are selected to have conduction bands  21 , 22  that are close to the impact ionization threshold of the semiconductor material contained in the primary conduction channel  6 . This enables a secondary channel. Since the width of the secondary conduction channel  2  is greater than the dimensions needed to induce quantization effects, a 2D-electron gas is only created in the quantum well  28  of the primary conduction channel. This leads to a tradeoff that diminishes switching speeds, but mitigates avalanche currents by allowing some of the carriers that would otherwise reach impact ionization thresholds in the primary conduction channel  28  to be diverted to the secondary channel  2 , which has higher ionization thresholds. The prior art instructs that the semiconductor material used in the primary and secondary conduction channels in an ultra-high speed FET be formed using epitaxial methods to produce crystalline semiconductor that maximizes the carrier mobility, velocity and mean free path. 
         [0065]    While the prior art teaches the use of multi-layer structures that induce 2D-electron gases within an ultra-thin plane of the ultra-high speed FET, the limitation restricting the primary conduction channel to thicknesses of 20-50 nm limits the overall currents that can be channeled through the high-electron mobility layers. Ultra-thin layers will cause high current densities that rapidly increase the probability of impact ionization and avalanche currents even at low power levels. Therefore, it is desirable to develop methods and embodiments that induce high electron mobility in semiconductor materials having thicknesses greater than 20-50 nm to reduce power densities in the high-speed layer. Higher currents can be achieved under the prior art, by creating multiple multi-layer structures comprising primary and secondary conduction channels. It is therefore desirable to produce a quantized conduction channel that has considerably greater thickness since the approach using multiple multi-layer structures has substantially higher cost and limited economic value when compared to a similar device that enables electron gas properties in a single semiconductor layer that is thicker than 20-50 nm. It is also desirable to develop methods and embodiments that enable electron gases in wider band gap semiconductor materials to better manage impact ionization thresholds. 
         [0066]    Reference is now made to FIGS.  5 A, 5 B, 6 A, 6 B to illustrate how the nanoscale microstructure controls enabled by LCD manufacturing methods are used to produce semiconductor layers that have three-dimensional (3D) electron gases. FIGS.  5 A, 5 B show cross sections of three dimensional microscopic volumes of polycrystalline semiconductor material  120  that consists of matrix of semiconducting grains  122  that have a maximum physical dimension  123  less than 50 nm in diameter, preferably a maximum physical dimension  123  in the range of 20-50 nm. The polycrystalline material may comprise an elemental semiconductor, such as silicon or germanium, a IV-IV semiconductor, containing a plurality of elements from column IV of the periodic table, or consists of III-V semiconducting compounds, more preferably compositionally complex III-V semiconducting compounds. Depending upon the device application, certain aspects of the present invention would favor the use of II-VI or IV-VI compound semiconductors, preferably compositionally complex II-VI or IV-VI compound semiconductors. 
         [0067]    Ordinarily, polycrystalline semiconductors have greatly reduced charge carrier mobilities due to the reduced mean free paths caused by the lattice dislocations encountered as the charge carrier attempts to navigate the grain boundary. However, maximum physical dimensions  123  in the range 20-50 nm are small enough to form quantum wells that induce quantization effects as each grain  122  of the polycrystalline semiconductor material  120  becomes a quantum dot within the bulk material when a chemically distinct material envelops the grain  122  at the grain boundaries  124 , 126 . The quantum dot thereby produces a three-dimensional (3D) electron gas within each grain  122 . Quantum tunneling mechanisms represent the fastest charge transfer mechanism across an energy barrier, occurring at femtosecond time periods, an additional preferred aspect of the present invention strengthens the energy barrier by optionally enveloping the semiconducting grains  122  with thin layers (2-10 nm thick, preferably 2-5 nm thick) of metallic grain boundary material  124  ( FIG. 5A ) or insulating grain boundary material  126  ( FIG. 5B ). The quantization effects induced by the phase-separated materials diffused into the grain boundaries are shown in FIGS.  6 A, 6 B.  FIG. 6A  depicts the energy band diagrams  130  of a 3D-electron gas, as viewed along any of the cross-sections A-A′, B-B′, C-C&#39;( FIG. 5A ), that are established by the junctions created when 20-50 nm polycrystalline semiconducting grains  122  are enveloped by metallic grain boundary material  124 , which has a thickness ranging from 1 nm to 10 nm, but is preferably in the range of 2-4 nm. The metal-semiconductor interfaces  131 A, 131 B, 131 C, 131 D form junction barriers  132 A, 132 B, 132 C, 132 D through the equilibration of the Fermi level  133  in metallic grain boundaries  134 A, 134 B and the semiconducting grains  135 A, 135 B, 135 C. The equilibration process will cause electrons in the metallic grain boundaries and holes in the semiconducting grains to collect at the interface. The strong depletion fields in the semiconductor regions will cause the conduction bands  136 A, 136 B, 136 C to bend thereby producing energy wells  137 A, 137 B, 137 C that quantize the electron energy levels  138  in the conduction bands to form a 3D-electron gas. At metal-semiconductor junctions, the height  139  of the junction barriers (φ B )  132 A, 132 B, 132 C, 132 D between the quantum energy wells  137 A, 137 B, 137 C generally given by: 
         [0000]        qφ   B   =q (φ m −χ)  (1)
 
         [0068]    where q is the electron charge, φ m  is the metal work function and χ is the semiconductor electron affinity. Conduction electrons injected into and contained within the quantized energy levels  138  will tunnel through the junction barriers (φ B )  132 A, 132 B, 132 C, 132 D at femtosecond transit speeds, which thereby makes very fast semiconductor switching speeds possible when these materials are configured in field effect transistor structures. The thin metallic grain boundary material  124  is a limitation in an FET-switched device as it will carry leakage currents that are undesirable in most applications. Therefore, it is preferable to form the polycrystalline semiconductor  121  that has electrically insulating or semi-insulating/semiconducting grain boundary material  126  enveloping the semiconductor grains  122  as depicted in  FIG. 5B . Abrupt junctions between the insulating grain boundary material  126  and the semiconductor grain  122  will produce characteristically different quantum well structures.  FIG. 6B  depicts the energy band diagrams  140  of a 3D-electron gas, as viewed along any of the cross-sections D-D′, E-E′, or F-F′ (see  FIG. 5B ) that are established by the junctions created when 20-50 nm polycrystalline semiconducting grains  122  are enveloped by an insulating grain boundary material  126 , which has a thickness ranging from 1 nm to 10 nm, but is preferably in the range of 2-5 nm. Alternatively, the insulator may alternatively be a wider band gap semiconductor to produce a heterojunction between the grain  122  and the grain boundary  126  materials. The insulator-semiconductor interfaces  141 A, 141 B, 141 C, 141 D form junction barriers  142 A, 142 B through the equilibration of the Fermi level  143  in insulating grain boundaries  144 A, 144 B and the semiconducting grains  145 A, 145 B, 145 C. The offsets in the conduction band edges  146 A and valence band edges  146 B between in the semiconductor and insulator regions will create energy wells  147 A, 147 B, 147 C in the semiconductor grains  145 A, 145 B, 145 C that quantize the electron energy levels  148  in the conduction bands  149  to form a 3D-electron gas. Similar quantization occurs in the hole energy levels  150  in the valence bands  151  of the semiconductor grains  147 A, 147 B, 147 C. Since the semiconductor material is polycrystalline, the charge carriers have very short mean free paths (20-50 nm) and ballistic conduction currents never achieve the high velocities needed to generate impact ionization. Furthermore, tunneling currents having femtosecond transit times dominate conduction mechanisms between quantum wells in this polycrystalline semiconductor material. These transport processes enable fast switching speeds and reduce the risk of avalanche breakdown as ballistic electrons never form and the quantum energy wells distributed throughout the solid effectively shield atoms in the crystal lattice from the conducting electrons. A 3D electron (hole) gas is formed since the grains are roughly spherical and trap electrons in a three-dimensional quantum energy well through which the electrons may tunnel in all directions. 
         [0069]    As discussed in greater detail below, thermodynamic and/or chemical incompatibility is required to phase separate the grain material from the grain boundary material while processing the polycrystalline grains. As shown in Tables I &amp; II ( FIGS. 11 and 12 ), insulating, semi-insulating or semiconducting grain boundary materials  126  that consist primarily of elements found in a column of the periodic table that is separated by at least 2 or 3 columns from the elements comprising the nanoscale polycrystalline grains achieves this thermodynamic/chemical incompatibility. Table I lists representative combinations of group IV and III-V compound semiconductors (left hand side) that can be used within grains  122  that are enveloped by insulating, semi-insulating, or wide band gap II-VI and/or I-VII semiconductor materials located in the grain boundaries  126 . Table II lists representative combinations of low band gap II-VI compound semiconductors (left hand side) that can be used within grains  122  that are enveloped by insulating, semi-insulating, or wide band gap group VI semiconductor materials located in the grain boundaries  126 . Similar relationships with respect to column ranking apply when enveloping semiconducting grains  122  with conductive grain boundary materials  124 . Since LCD manufacturing methods enable the chemical integration of high chemical complexity materials, it should be clearly understood that III-V and II-VI semiconducting compounds need not be limited to binary compositions, but can easily comprise 3 or more elemental components. 
         [0070]    The principal advantage afforded by these polycrystalline semiconductors is that devices having arbitrarily thick conduction channels can be easily constructed in contrast to the prior art in which the primary conduction channels  6  are limited to 20-50 nm layer thicknesses as shown in  FIG. 1 .  FIG. 7  depicts a significant aspect of the present invention, which provides means to construct a electrically active field, field effect transistor (FET) device  160  that can carry more substantial currents than the prior art. Since polycrystalline semiconductor reduces the mean free path of conduction electrons and the associated risk of avalanche breakdown caused by high ballistic velocities, the 3-D electron (and hole) gas(es) produced therein do not need to be confined in thin primary conduction channels  6  surrounded by one or more wider band gap semiconductor layers  7 , 8 , and  3 , 4 . Under the present invention, the primary conduction channel  161  may have polycrystalline semiconductor layer thickness ranging from 20 nm to 10 microns (μm), preferably greater than 50 nm and most likely 1-2 μm, thereby allowing much higher currents to be modulated at significantly lower current densities. Since the present invention forms the electron gas by the nanoscale microstructure of the semiconductor layer itself rather than the quantum-size effects induced by the energy barriers between semiconductors, it enables the use of wide band gap material in the conduction channel, such as silicon (E gap =1.11 eV) or gallium arsenide (E gap =1.43 eV) that is less susceptible to impact ionization than the low band gap counterparts like indium antimonide (E gap =0.17 eV). In cases where it might be advantageous to insert a low band gap material in a conduction channel thicker than 50 nm, the conduction channel may optionally have additional layers  162 , 163  comprising a wider band gap semiconductor material inserted between it and the substrate  164  and/or the gate electrode  165 . Voltages applied to the gate electrode  165  are used to vary electric fields through the gate oxide  166  to modulate current flow in the primary conduction channel  161  between the source  167  and the drain  168  regions. Electrical contact is made to the source  167  and drain  168  regions using an ohmic source electrode  169  and drain electrode  170 , respectively. 
         [0071]    Since the modulated currents multilayer 2D-electron gas structures instructed by the prior art limit high-speed current transport to primary conduction channel(s)  6  that are 20-50 nm thick, forty (40) to one hundred (100) such layers would be required to transport equivalent currents in a single two (2) micron thick 3D-electron gas primary conduction channel  161  described by the present invention. The high-speed quantum dot field effect transistor may be integrated in any circuit using LCD methods, apparatus, and processes, including, but not limited to, power management devices or silicon carriers that are used in high-speed computing processes or radio applications. 
         [0072]    Reference is now made to FIGS.  8 A, 8 B, 8 C, 8 D to describe how liquid chemical deposition (LCD) methods are used to form the polycrystalline 3D-electron gas semiconductor layers  161 . de Rochemont et al. &#39;112, incorporated herein by way of reference, describes the apparatus?, processes used by the LCD process to form an amorphous layer  171  on a substrate  172 . The substrate  172  may comprise an appropriately doped semiconductor wafer or a semiconductor layer. The amorphous layer  171  is formed on the substrate  172  by decomposing an aerosol spray of low volatility liquid metalorganic precursors consisting of a stoichiometric mixture of the desired semiconductor compound, its electronic dopants (if desired), and its grain boundary materials in an inert or reducing gas environments. The substrate  172  needs to be heated to a temperature that will pyrolyze liquid precursor compounds having the highest decomposition temperature, typically 200° C. to 500° C., preferably 300° C. to 400° C. The inert or reducing gas atmosphere may comprise nitrogen or noble gases, hydrogen, and/or reducing partial pressure ratios of carbon monoxide and carbon dioxide (by means of applying an aerosol spray of liquid metalorganic precursors to an appropriately doped semiconductor layer or wafer which functions as the substrate  172  ( FIG. 8A ). The amorphous layer may comprise an elemental semiconductor with electrical and other dopants, or it may be a compound semiconductor with electrical and other dopants. The LCD process enables the amorphous layer to have a precise ratio of chemical components that is compositionally uniform at the atomic scale. Spray deposition is followed by a bake out step that heats the substrate and deposit to temperatures between 400° C. and 600° C. for 2-20 minutes to remove any residual organic material that did not pyrolyze during the aerosol spray deposition step. The presence of any liquid species in the deposit will accelerate the deterioration of atomic scale chemical uniformity during subsequent annealing steps. 
         [0073]    A plasma annealing step is then used to render the amorphous layer  171  into a polycrystalline layer  173  that has uniform microstructure with grain sizes  174  ranging between 20-50 nm. Other thermal processing methods may be used to render the amorphous deposit into a polycrystalline state, but rapid thermal annealing process, and plasma annealing processes in particular, are preferred. The substrate  172  and deposit  171  may be pre-heated to temperatures in the range of 40° C. to 400° C. during the ionized plasma annealing step. Argon gas is the primary ballast used in the plasma annealing step, with additional gas additives consisting of nitrogen and/or carbon monoxide and carbon dioxide not exceeding 20% partial pressures. Total atmospheric pressures in the range of 1500 to 5000 mTorr, with power settings ranging from 50 W to 300 W for periods of 5 to 60 seconds are preferred for generating nanoscale polycrystalline semiconducting grains enveloped with a distinct phase grain boundary material. 
         [0074]    It is desirable to select metallic species that will be driven towards the grain boundaries by thermodynamic processes during the annealing step to form metallic grain boundaries. In the early-stages of crystalline nucleation, cooperative forces will create crystalline fields that atomically organize the majority elements in the amorphous deposit  171  into its thermodynamically most favored crystalline phase. The cooperative forces will be driven by the majority chemical concentrations, causing chemically compatible elements to be drawn into the crystal nucleation process while expelling chemically incompatible elements to the grain boundaries. For example, if silicon is the majority chemical element, present in the deposit at levels exceeding 99.99 mol %, the crystalline fields that build during the nucleation process will favor the incorporation of elements that have similar charge and molecular orbital orientations, such as germanium. It is therefore desirable to select grain boundary materials from metallic elements that have incompatible charge and orbital characteristics to the semiconductor compound being formed within the grain, such as those shown in Tables I &amp; II. Elements that are located in the columns of The Periodic Table furthest away from the column in which the semiconducting elements are drawn from satisfy this requirement. Therefore, metalorganic precursors to alkali metals or alkaline earth metals, in concentrations of 0.0001 to 0.5 mol %, are added to the liquid precursor solution used to form the amorphous deposit when it is desirable to form metallic grain boundaries  175  in the polycrystalline deposit  173 . Alkali metals are preferred over alkaline earth metals. Halogenated metalorganic precursors to alkali metals, alkaline earth metals, or transition metals are added to the liquid precursor solution when it is desirable to form insulating grain boundaries  176  that comprise any of the I-VII grain boundary materials depicted in Tables I and II in the polycrystalline deposit  173 . Precursor molecules  177  essentially “carry” a metallic element  178  attached to an organic molecule that decomposes on the surface where the metallic element  178  is eventually deposited. Halogenated precursors will substitute one or more of the hydrogen elements  179  in the organic molecule with a halide element  180  from the group: fluorine, chlorine, iodine, or bromine. Halogenated alkali or alkaline earth metal precursors allows the elemental constituents of insulating compounds, comprising either a singular alkali or alkaline earth halide or a plurality of alkali or alkaline earth halides, to be transported to the deposition surface and integrated into the amorphous deposit and driven into the grain boundary regions  176  in a subsequent plasma annealing step. As explained in greater detail within application &#39;405, silicon carbide or aluminum nitride material phases can be introduced to the amorphous deposit  171  by forming a colloidal suspension of liquid metalorganic precursors and silicon carbide or aluminum nitride nanoparticles. These nanoparticle carbide and nitride phases will migrate to the grain boundaries during plasma annealing when their molar concentrations are held between 0.0001 mol % and 0.75 mol %. 
         [0075]    A specific advantage to the present invention is its ability to use the 3D electron gases generated by the nanoscale polycrystalline semiconductors to increase the carrier mobility within a specific layer or in a plurality of layers, which is not possible under the prior art. In the prior art described by Phillips &#39;292, a 2D electron gas is generated by forming quantum wells by sandwiching a layer of low band gap semiconductor, such as indium antimonide (InSb, E gap =0.17 eV), between epitaxial layers of higher band gap semiconductors. (See  FIGS. 1&amp;2 ). Low band gap semiconductors such as InSb can have very high charge carrier mobility, as shown in  FIG. 4 , but they are also susceptible to avalanche currents due to impact ionization processes that cause conduction band electrons accelerated by electrical drift to knock valence band electrons off of the atoms to which they are bound. This process generates excess conduction band electrons that generate runaway switching currents which compromise performance. The 2D quantum wells create a quantized energy band structure within the planar low band gap semiconductor that effectively shields the valence band electrons from the conduction electrons travelling through the layer at ballistic velocities. Additional layers  3 , 4  of wider band gap semiconductor  24 , 25  can be added to further mitigate impact ionization processes. The 2D quantum wells shield valence band electrons and minimize electromagnetic interactions between the free electrons and the valence band electrons bound to the atoms forming the semiconductor material. The shielding reduces the conduction electron&#39;s effective mass, (“inertia”), which makes it more responsive to drift transport mechanisms under the influence of an applied electric field. 
         [0076]    As mentioned above, tunneling processes represent the fastest electron transport mechanism. Tunneling processes are possible between adjacent quantum wells (not shown), but not within a low band gap semiconductor layer since there are no energy barriers within layer forming the bottom of the well. (Adjacent quantum wells can be visualized by imagining a plurality of multilayer structures in the vertical direction of  FIG. 1 .) The principal benefits to a planar 2D electron gas is a lowered electron (and hole) effective mass and reduced susceptibility to impact ionization within a very thin (20-50 nm) layer of a low-band gap semiconductor layer. 
         [0077]    As mentioned above, the 3D quantum wells of the present invention interject an energy barrier at the boundary of every grain. Therefore, the mean free path of any conduction electron is limited to the nanoscale dimension of the grain (20 nm to 50 nm). The drifting electron will then encounter a thin (2 nm to 10 nm) energy barrier through which it will tunnel. The combination of reduced mean free path (reduced impact ionization) and tunneling currents in the direction or primary drift currents allows all types of semiconductor materials to support fast transport processes in any direction, without the restriction of limiting the modulated current to a 20-50 nm layer. 
         [0078]    This advantage is particularly important in power FET devices, opto-electronic or photonic devices as any of the layers  161 , 162 , 163 , 164  (see  FIG. 7 ) may be formed as an arbitrarily thick semiconducting 3D electron gas. Additionally, each individual layer  161 , 162 , 163 , 164  may be composed of semiconducting grains having an energy band gap that is distinct from the band gap in a neighboring polycrystalline semiconducting layer. This aspect of the invention is particularly beneficial to device structures where switching speeds are limited by reduced carrier mobility in bulk semiconducting layers by virtue of the layer&#39;s electronic doping, as is the case with the insulated gate bipolar transistor (IGBT) where the p + -doping layer will limit switching speeds.  FIG. 9  depicts a cross-sectional view of an IGBT device  200  integrated on the silicon chip carrier, which may optionally include the semiconductor carrier substrate  202  and electrode  204  that functions as a ground and a heat sink. LCD enables the insertion of a very thin amorphous layer  206  that allows a single crystal p + -type semiconductor drain layer comprising a semiconducting 3D electron gas layer  208  to be deposited upon the drain electrode  204 , which may also comprise a 3D electron gas layer. A p-n junction  210  forms between the p + -type semiconductor drain layer  208  and an n-type semiconductor layer  212  that may optionally consist of 3D electron gas polycrystalline material. The n − -type semiconductor layer is electrically patterned with p-type subchannel  214 A, 214 B, 214 C and n+-type dopant profiles  216 A, 216 B, 216 C, 216 D that are in electrical communication with the source electrode  218 . The insulated gate electrode  220  modulates inversion carrier populations in a channel  222  that allow currents to flow from the drain  208  to the source electrode  218 . The gate electrode  220  is encapsulated within a low loss high-dielectric breakdown insulating material  224 A, 224 B, preferably an amorphous silica insulating material. Any or all of the semiconductor layers may consist of a nanoscale engineered polycrystalline semiconductor modified to generate a 3D electron gas. Since LCD deposition methods also enable three dimensional monolithic materials integration, vertical conduction channels consisting of 3D electron gas semiconductor regions  226 A, 226 B, 228 A, 228 B that may be optionally added to the device structure, wherein each of the 3D electron gas semiconductor regions  226 A, 226 B, 228 A, 228 B may comprise polycrystalline grains having energy band gaps that differ from the energy band gaps in any of the adjacent semiconductor material in the IGBT device  200 , thus forming a plurality of heterostructures within the three-dimensionally pattered monolithic structure. 
         [0079]    A final embodiment is depicted in  FIG. 10 , which depicts a semiconducting carrier  250  that consists of a power management module  252  monolithically integrated upon the surface of the carrier substrate  254 , one or more semiconductor die  256  mounted thereupon, and an opto-electronic or photonic device  258  that contains a 3D electron gas semiconducting layer  260  embedded within it. 
         [0080]    It is readily understood that the quantum well technology and manufacturing methods described herein may be easily applied to any other form of quantum well devices, including but not limited to multiplexers, signal encoders, and sensors. It is further readily understood that the devices described above embody methods of manufacture and methods of operation which are also new and non-obvious with respect to the prior art. 
         [0081]    The present invention is illustratively described above in reference to the disclosed embodiments. Various modifications and changes may be made to the disclosed embodiments by persons skilled in the art without departing from the scope of the present invention as defined in the appended claims.