Patent Application
20090243043
The present invention relates to a method of growing thick single-crystal compound semiconductor material and the material thus produced, for example by material hydride vapour phase epitaxy (HVPE) deposition using nanostructure compliant layers produced by molecular beam epitaxy (MBE), chemical vapour deposition (CVD), metalorganic chemical vapour deposition (MOCVD), which is also known as metalorganic vapour phase epitaxy (MOVPE) and HVPE.
Wide band-gap GaN and related materials are recognized to be among the most attractive compound semiconductors for use in a variety of devices. They are adapted for optoelectronic and microelectronic devices which operate in a wide spectral range, from visible to ultraviolet and in the high temperature/high power applications area. The main advantages of nitride semiconductors in comparison with other wide-band-gap semiconductors is their low propensity to degrade at high temperature and high power when used for optical and microelectronic devices. Meanwhile, low-dimensional quantum confinement effects (i.e. in quantum wires and dots) are expected to become one of the foremost technologies for improving optical device performances. Fabrication of a variety of low-dimensional structures in III-V nitrides has been undertaken using methods such as etching, re-growth, overgrowth on selected areas, growth on tilted substrates, self-organization process, etc.
Despite the technological advances of the last few years, one of the key obstacles preventing further developments in GaN devices is the lack of high quality and commercially available low-cost, free-standing GaN substrates. Alternative substrates, such as sapphire and SiC are commonly employed in nitride-based devices. As a result of lattice mismatch and large differences in the thermal expansion coefficients between the deposited film and substrate (heteroepitaxy), a very high (109 to 1010 cm−2) density of threading dislocations and serious wafer bending/cracking, induced by undesired residual strain, occurs in the grown nitride layers. These factors can significantly affect the performance and lifetime of nitride-based optoelectronic and microelectronic devices.
Epitaxial lateral overgrowth technique (so-called ELOG and its modifications facet initiated epitaxial lateral overgrowth (FIELO) and Pendeo (from the Latin to hang or be suspended)) is the most widely used approach employed for suppressing bending and a significant fraction of the threading dislocations in the material. Laterally overgrowing oxide (or metal) stripes deposited on initially-grown GaN films has been shown to achieve about two orders of magnitude reduction in the dislocation density, reducing it to the 107 cm−2 level. However, the low defect-density material only occurs in the wing region, located in the coalescence front, and represents only approximately one fifth of the whole wafer surface area. Large coalescence front tilting and tensile stress are both present in the overgrowth region.
Low defect-density free standing GaN is currently one of the materials of choice to achieve the desired specification for optoelectronic and microelectronic devices. Bulk (melt or sublimation) and hydride vapour phase epitaxy (HVPE) are the two main techniques for growing free standing and low defect-density GaN. Bulk GaN growth techniques operating at a very high pressure of ˜15 kbar have been successful in growing low dislocation density (<107 cm−2) material. Unfortunately, this technology suffers from a low growth rate and is limited to small diameter substrates, making them very expensive and uneconomic for commercial manufacturing. The record nitride laser lifetime of 15,000 hours under CW-operation at the 30 mW output level has recently been demonstrated by Nichia Chemicals Inc., using the HVPE grown substrate. HVPE is clearly one of the most promising techniques available to provide low defect-density GaN and large diameter commercial free-standing GaN substrates.
HVPE is a reversible equilibrium-based hot-wall process with several advantages: (1) high growth rate (up to 100 μm/hr—more than 100 times faster than that of the MOCVD and MBE methods); (2) low running costs; (3) the mutual annihilation of mixed dislocations lowers the defect densities in thick GaN. However, the HVPE technique still has the same inherent problems due to its growth on a foreign substrates. Therefore, the growth of thick GaN using HVPE in general has to overcome two critical issues; firstly, to reduce the bending and cracking of initial GaN thick films (30-100 μm) on foreign substrates and secondly, to minimize the defect density of GaN.
The cracking of thick GaN film, due to the use of foreign substrates, depends on the growth and cooling conditions. The critical thickness for crack appearance in GaN can be improved from a typical value of 10-15 μm for GaN grown conventionally by the HVPE directly onto sapphire substrates, to 40-80 μm-thick crack-free layers by the use of reactively sputtered AlN buffer layers, or by employing ZnO buffer layers. However, even this thickness is not sufficient for safe handling during substrate separation. To further reduce the cracking in thicker GaN films in the initial growth, other growth techniques such as ELOG, growth on patterned substrates, re-growth with molten Ga interfacial layers, use of substrates better matched to GaN, and the use of thinned and mechanically weakened sapphire substrates have also been exploited.
To reduce defect density (mainly threading dislocations) and strain, and to improve the surface morphology of the thick GaN films grown by HVPE, various techniques have been employed, for example ELOG, growth under lower reactor pressure and growth with TiN intermediate layers, or deep inverse pyramid etch pits on weakened Si, GaAs and other III-V single crystal wafers. However, the growth processes using these techniques are tedious, time consuming and expensive. The GaN thus produced still has the major disadvantages of bending and undesired residual strain.
Various vapour deposition methods suitable for growing GaN materials are described in U.S. Pat. No. 6,413,627, U.S. Pat. No. 5,980,632, U.S. Pat. No. 6,673,149, U.S. Pat. No. 6,616,757, U.S. Pat. No. 4,574,093 and U.S. Pat. No. 6,657,232. Other publications relating to such methods include:
It is an object of the present invention to provide a method of growing high-quality flat and thick compound semiconductors which at least partially overcomes the problems discussed above. In this context, a “thick” semiconductor is one that is substantially self-supporting, typically of thickness greater than about 50 μm.
In accordance with the present invention there is provided a method of producing single-crystal compound semiconductor material comprising:
Preferably, the compound semiconductor material is selected from the group consisting of III-V and II-VI compounds.
Preferably, the substrate material is selected from the group consisting of sapphire, silicon, silicon carbide, diamond, metals, metal oxides, compound semiconductors, glass, quartz and composite materials. Substrates of different crystal orientation can be used, for example: c-plane sapphire, γ-plane sapphire, m-plane 4H and 6-H SiC. By using nanostructures fabricated on substrates of different crystal orientation, high quality, low strain and low defect density non-polar and polar compound semiconductor layers can be overgrown. For the growth of normal polar materials such as c-plane GaN, the crystal orientation of the substrate can be c-plane sapphire. For the growth of non-polar materials such as a-plane or m-plane GaN, the crystal orientation of the substrate can be γ-plane sapphire or m-plane 4H— or 6H—SiC respectively.
If γ-plane sapphire is used as the substrate, non-polar a-plane GaN can be grown using nanostructure compliant layers. The a-plane GaN thus grown will have very low strain and low defect density. M-plane GaN can be grown on (100) LiAlO2, m-plane 4H— or 6H—SiC using nanostructure compliant layers.
The substrate material may also be selected from the group consisting of conductive substrates, insulating substrates and semi-conducting substrates. The substrate may comprise a compound semi-conductor material previously produced by a method in accordance with the first aspect. The quality of the compound semi-conductors produced by the invention is such that they may be used as seed substrates for future growths. For use as a substrate, the semiconductor material may be sliced to the required thickness if necessary, and will usually be lapped and polished before use.
Step (a) may include the step of growing the compound semiconductor nanostructure onto the substrate. In other words, the substrate and nanostructure formation is prepared specifically to grow the compound semiconductor. Alternatively, the substrate and nanostructure formation may be pre-prepared. For example, the formation may be re-used after removal of a previously grown semiconductor. When growing the nanostructure, at least one nano-island may be created on the substrate material prior to growing the nanostructure. This step facilitates growth of the nanostructures. The nano-island may be created by treating the substrate by at least one of nitridation, sputtering, metal deposition and annealing, CVD and MOCVD.
The nanostructure may be grown using an HVPE method, or alternatively a CVD method, a MOCVD method or an MBE method.
The nanostructure may be either un-doped, or doped with n- or p-type dopants.
The nanostructure may be grown with single doped or undoped material, or with the combination of un-doped and doped steps, or n-doped and p-doped steps.
In particular, the nanostructure may include a p-type region proximate the growth surface. The inclusion of such a region may assist with removal of the overgrown semiconductor, for example when using an anodic electrochemical selective etch process.
Preferably, the nanostructure comprises a material selected from the group consisting of GaN, AlN, InN, ZnO, SiC, Si, and alloys thereof.
The compound semiconductor material may optionally comprise a different material from the nanostructure.
The epitaxial lateral overgrowth of compound semiconductor material may be carried out by an HVPE method.
The epitaxial lateral overgrowth of compound semiconductor material may be either undoped, or n- or p-type doped.
The epitaxial lateral overgrowth of compound semiconductor material may be time-modulated.
Advantageously, step (b) is performed while rotating and/or lowering the substrate.
The grown compound semiconductor material may be separated from the substrate by rapidly cooling the material. Alternatively, it may be mechanically separated, or separated from the substrate by wet etching or electrochemical etching, or by laser ablation. In the case of laser ablation, the laser may be directed toward the substrate-semiconductor material interface from the side of the structure, or alternatively up through the substrate.
The grown compound semiconductor may be sliced to produce a semiconductor layer of preselected thickness.
In accordance with a second aspect of the present invention there is provided a thick single-crystal compound semiconductor material grown using the method in accordance with the first aspect.
In accordance with a third aspect of the present invention there is provided a substrate material having a compound semiconductor nanostructure grown onto it to provide an epitaxial-initiating growth surface. This enables compound semiconductor material to be grown onto the surface using epitaxial lateral overgrowth in accordance with the first aspect of the present invention. The nanostructure may include a p-type region proximate the growth surface.
An exemplary method in accordance with the invention utilizes HVPE to grow high quality flat and thick compound semiconductors onto foreign substrates using nanostructure compliant layers. Examples of suitable nanostructures include nanocolumns (also known as “nano-rods”) of substantially constant diameter along the majority of their length, or other structures, for example pyramids, cones or spheroids which have varying diameter along their major dimensions. For simplicity, the following description will discuss the use of nanocolumns, however it should be realised that other suitable nanostructures such as those mentioned above may be also be used, and indeed may be advantageous for certain applications. Nanocolumns of semiconductor materials can be grown on any foreign substrates by MBE, CVD, MOCVD (MOVPE) or HVPE methods. Such nanocolumns may typically have a diameter of about 10 to 120 nm. Mechanical confinement in nanocolumns grown on foreign substrates provides a mechanism for the stress and dislocations to be localized in the interface between the nanocolumns and the substrate. Thus growth will lead to the top part of the nanocolumns being nearly free of stress and dislocations. Further growth of continuous compound semiconductor thick films or wafer can be achieved by epitaxial lateral overgrowth using HVPE. Compound semiconductor thick film and wafer bending due to the thermal expansion coefficient difference between the compound semiconductor materials and the substrate can be minimized by a balanced dimension of the nanocolumn and air gap, which functions to relax the biaxial strain. Both thick and flat compound semiconductor films can therefore be grown using this technique. Localized stress between the nanocolumn and substrate also allows the thick semiconductor, for example GaN to be readily separated from the substrate during rapid cooling. An anodic electrochemical selective etch process for p-GaN can also be used to separate the GaN film from the substrate when a thin p-GaN is grown on the tip of the nanocolumn before the epitaxial lateral overgrowth. The thick GaN may then undergo slicing, grinding, lapping, and polishing processes to produce polar and non-polar compound semiconductor wafers.
The growth processes provided by the invention can be applied to the family of III-V nitride compounds, generally of the formula InxGayAl1-x-yN, where 0≦x≦1, 0≦y≦1, and 0≦x+y≦1, or other suitable semiconducting nitrides. Group II-VI compounds may also be suitable for production through the methodology of the present invention. The semiconductor may for example comprise materials such as GaN, AlN, InN, ZnO, SiC. Throughout the following description, the invention is described using GaN as an example of an epitaxial III-V nitride layer as the semiconductor material for convenience, though any suitable semiconducting material may be used.
The hydride-vapour phase epitaxy (HVPE), also called chloride transport chemical vapour deposition, of GaN is a relatively well-established process based on the gaseous transport of the group III and group V elements to the deposition zone of a growth reactor. In this technique Cl is used to transport the group-III species instead of organometallic sources in the MOCVD technique. This has a distinct advantage in that large growth rates (up to 120 μm/hr) can be achieved by this technique over the MOCVD or the MBE methods (≦2 μm/hr). In contrast to MOCVD, which is a non-equilibrium cold-wall reactor-based technique, HVPE is a reversible equilibrium-based process in which a hot-wall reactor is employed. The typical growth procedure is as follows. Sapphire, silicon carbide, zinc oxides or other compatible substrates are inserted into the deposition zone of the growth chamber and heated. When the final growth temperature is reached the NH3 flow is started. After a period to allow the NH3 concentration to reach a steady-state value, HCl flow is started to provide transport of the gallium chloride (GaCl), which is synthesized by reacting HCl gas with liquid Ga metal in the Ga zone at 800-900° C. via the reaction: 2HCl(g)+2Ga(l)→2GaCl(g)+H2(g). An alternative method of synthesis is by reacting Chlorine gas with Ga metal around 125° C. Then gaseous GaCl is transported from the Ga zone to the deposition zone to react with NH3 at 900-1200° C. to form GaN via the reaction GaCl(g)+NH3(g)→GaN(s)+HCl(g)+H2(g). The thickness of deposited GaN layer using this technique is typically up to 800 μm. Another major advantage of the HVPE growth method is the mutual annihilation of mixed dislocations lowering the defect densities in thick GaN. These characteristics make HVPE an ideal technology for manufacturing free-standing GaN and other related III-V nitrides substrates at low cost.
The growth temperature in the HVPE method is rather high (˜1000° C.) and, hence, one major problem of growing thick GaN film is the possibility of cracks and lattice defects due to the use of foreign substrate, for example sapphire. It follows that there may also be mismatch in the lattice constants and thermal expansion coefficient between the GaN layer and the substrate).
The present invention provides a novel method for growing flat, low defect density, and strain-free thick semiconductor on any foreign substrates using a nanostructure compliant layer with an HVPE growth process. The use of GaN nanocolumns, for example, as the compliant layer to grow thick GaN has several advantages. The mechanical confinement occurs between the interface of the nanocolumns and substrate due to the small diameter and the high aspect ratio of the column (height versus diameter). The stress and dislocations are mostly localized in the interface between the GaN nanocolumns and the substrate. Thus growth leads to the top part of the GaN nanocolumns being nearly free of stress and dislocations. In addition, the defects caused by the mosaic structure in conventional GaN films, arising from a spread of initial island misorientations can be minimised, since badly misoriented nanocolumns eventually grow out, improving the general alignment. The topography of nanocolumns with a narrow air gap permits coalescence with a very thin overgrown layer. Typically only ˜0.2 μm thickness is required for continuous overgrown GaN layers. With all the advantages described above, high-quality thick GaN can therefore be grown on this nanocolumn compliant layer, and has very little tilting in the coalesced front either on top of the nanocolumns or on top of the air gap in comparison with other ELOG or Pendeo processes.
GaN wafer bending due to the thermal expansion coefficient difference between the GaN and the substrate is also minimized by a balanced dimension of the nanocolumn and air gap, which functions to relax the biaxial strain. Thick and flat GaN films can therefore be grown using this technique, including so-called GaN “boules” which may be sufficiently thick to be sliced into multiple wafers. Localized stress between the nanocolumn and substrate also allows the thick GaN to be readily separated from the substrate during the rapid cooling, particularly if a tensile-stressed thin layer is grown between the nanocolumn and the substrate. An anodic electrochemical selective etch process for p-GaN can also be used to separate the GaN film from the substrate. The thick GaN, i.e. a boule, may then undergo slicing, grinding, lapping, and polishing processes as appropriate to produce standard thickness (˜250 μm) GaN wafers in a process designed to produce commercial quantities. A wafer produced in this way may be used as the substrate for a further process in accordance with the present invention.
GaN nanocolumns can be grown by MBE using an RF-plasma nitrogen source. If sapphire substrate is used, a nitridation process is preferably conducted first. AlN nucleation layers need to be deposited at a temperature higher (˜850° C.) than that of the normal GaN growth process. The purpose of this higher nucleation temperature is to achieve a desired ratio of the top surface area versus the base, which in turn initiates the nanocolumn growth. During growth, the nitrogen flow rate and RF input power can be optimised to produce high density island structures. The targeted island features typically have a height of 5-10 nm and density of ˜1010 cm−2. GaN nanocolumns will typically be grown under a N-rich atmosphere, as RF-MBE growth under Ga-rich conditions does not result in nanocolumn growth. The MBE growth parameters may be optimised in order to achieve the desired dimension, aspect ratio, and density of nanocolumns. In-situ Reflection High Energy Electron Diffraction (RHEED) may be used to monitor the 3D island nucleation and GaN nanocolumn growth. To further enhance the growth of nanocolumns with smooth side walls, n-type Silicon doping is preferably employed, since Si doping can significantly enhance the growth rate along the (0001) direction. The morphology of the top facet of nanocolumns can also be manipulated by doping, using different nitride alloys and growth temperature.
Nanocolumns can also be grown using CVD, MOCVD, and HVPE methods. In a MOCVD growth method, catalytic vapour-liquid-solid growth mechanism using In or Ni as the catalyst to initiate the growth combined with pulsed injection of metalorganics and NH3 are used to obtain controlled growth of GaN nanocolumns. To further refine the control of the top facet morphology, the dimension, aspect ratio and density of nanocolumns, process parameters in MOCVD such as various doping, reactor pressure, reactor temperature, III/V ratio and injection pulse patterns are varied.
GaN nanocolumn growth in HVPE is ideally carried out at very low growth temperature (<500° C.) to minimize the surface diffusion and lateral growth.
Both GaN nanocolumn templates and GaN nanocolumn templates with initial thin continuous GaN grown by ELOG using MBE or MOCVD can be loaded for the thick GaN ELOG growth using HVPE. The observed evolution of the ELOG GaN morphology is sensitive to the growth parameters, in particular the temperature and pressure. This infers that the ELOG morphology can be seriously affected by the temperature distribution across the wafer, with resulting differences in the height and morphology of ELOG GaN. Thus temperature uniformity is a strong requirement for HVPE growth. In the HVPE system the temperature uniformity can be controlled using multi-zone substrate heaters combined with lower temperature hot-wall furnace heating systems. The substrate holder may also be equipped with a lowering mechanism to maintain the same distance between the gas outlet and the substrate surface. Process parameters such as reactor temperature, pressure, total gas flow, and V/III ratio may be systematically varied for the growth of thick flat films.
The separation of the grown GaN can be achieved by the following methods. In brittle materials such as sapphire and III-V nitrides, cracking may occur easily when the tensile stress exceeds a critical value. The cracking of the epitaxial layer under compressive stress requires much higher stress and tends not to occur in normal circumstances. GaN nanocolumns with their inbuilt flexibility, due to their aspect ratio and nano-dimensions, will develop minimal internal stress. In order to separate the thick GaN from the substrate with ease and reproducibility, an AlN nucleation layer, under tensile stress, with a critical dimension may be used. Rapid cooling or mechanical twisting will push the local stress to exceed the critical value to separate the thick film. Another method of separating the GaN from the substrate is to use anodic electrochemical etching. In this case, a thin p-GaN layer can be grown on top of the nanocolumn before the epitaxial lateral overgrowth for thick GaN. Using a suitable electrolyte and bias voltage results in p-GaN being selectively etched off, to leave the n-GaN untouched.
Spectroscopic reflectance (SR) allows the measurement of the superposition of lateral interference and vertical interference which can provide both strain and thickness information on the layers. Reflectance measurements at the same wavelength as pyrometry allow the determination of the actual emissivity of the wafer, which in turn enables measurement of the true temperature of the wafer. SR can also help to measure and define the stage of the formation of 3D nucleation islands and the coalescence in the nanocolumn and ELOG growth process. This is essential for the control of nanocolumns and thick film growth.
Specific embodiments of the invention will now be described with reference to the accompanying drawings, in which:
To illustrate the invention, various practical Examples using techniques in accordance with the inventive method are described below.
A c-plane-oriented sapphire substrate of about 2 inches (5.08 cm) in diameter is loaded onto the substrate holder of the HVPE vertical reactor described above and shown in
For the epitaxial lateral overgrowth, the pressure of the growth chamber is raised to 700 mbar. Gas delivery of NH3 is raised to 2000 sccm, then the substrate's temperature is ramped to about 1050° C. in 20 minutes. The GaN growth step is continued until a GaN epitaxial layer of sufficient thickness is produced. During the growth, the substrate is lowered down through the rotation lowering mechanism of the substrate holder to maintain the constant distance between the gas frits and the substrate. For the growth with the V/III ratio set between 10 and 40 in the vertical HVPE reactor of
In the nitride growth termination, GaCl gas is switched off, flow of NH3 is maintained at the same level and N2 flow is increased to make up the steady total gas flow. The substrate cool-down is controlled in a process steps of higher than 50° C./min between 1050° C. and 500° C. The flow of NH3 is then switched off below the temperature of 500° C. The cool-down continues with a rate less than 100° C./min between 500° C. and room temperature. During this time, the gas heater maintains the temperature at about 350° C. and the substrate is lowered down from the chamber to maintain the cool-down rate at less than 100° C./min.
Once the substrate is cooled and removed from the reactor, the sapphire substrate can be seen totally or partially separated from the thick GaN epitaxial layer. A further mechanical twist is sufficient to separate the partially separated GaN layer.
In this example, the nanocolumn HVPE growth process described in Example 1 above is replaced by the following pulsed MOCVD growth process. A thin layer, around 5 nm, of Ni is deposited by electron beam evaporation onto the c-plane oriented (0001) sapphire substrate. The Ni coated sapphire is then loaded into a MOCVD reactor. The substrate is heated to about 800-850° C. under the N2 flow to form dispersed Ni islands on the surface. H2 is used as the carrier gas and the reactor pressure is kept at 100 mbar. NH3 flow is 1000 sccm and Trimethylgallium (TMG) flow is 36 sccm. The substrate temperature is then lowered to around 700-800° C. Vapour-liquid-solid (VLS) growth commences with the pulsed injection of 2-6 seconds TMG, followed by a 2-6 second delay, then a further 2-6 seconds NH3. During the TMG injection, NH3 is switched off. During the NH3 injection, TMG is switched off. This causes reduced pre-mixing particulates to be formed using this process. The lower temperature, compared to Example 1, significantly reduces the lateral diffusion. The nanocolumn template is then dipped into HCl solution to remove dispersed Ni metals on the template. GaN nanocolumns grown for one hour this way typically have diameters of 90-100 nm and heights of around 680 nm.
Here, the nanocolumn HVPE growth process described in Example 1 above is replaced by the following pulsed MOCVD growth process. A surface nitridation step is carried out for about 5 minutes with the reactor pressure at about 100 mbar, substrate temperature about 800° C., and NH3 flow at about 1200 sccm. The substrate temperature is then raised to about 850-900° C. The NH3 flow is adjusted to about 1000 sccm and TMAl was adjusted to about 15 sccm. High density AlN islands growth is carried out using the pulsed injection of 2-6 seconds TMAl, followed by a 2-6 second delay and then 2-6 seconds NH3. The AlN growth typically takes about 10-30 minutes. An AlN islands density of around 1010 cm−2 may be achieved by this method. The substrate temperature is then lowered to around 700-750° C. NH3 flow is set to about 1000 sccm and Trimethylgallium (TMG) flow to about 36 sccm. GaN nanocolumn growth is carried out under H2 with the pulsed injection of 2-6 seconds TMG, followed by a 2-6 second delay and then 2-6 seconds NH3. GaN nanocolumns 12 grown for about two hours this way typically have diameters of around 60-120 nm, and heights of around 800-1000 nm.
Here, the nanocolumn HVPE growth process described in Example 1 above is replaced by an MBE growth process. The active nitrogen species are supplied by a radio frequency (RF) plasma source using high purity N2 as the feeding gas. Al and Ga are supplied from effusion cells using high purity metals. The N2 flow is set at about 2 sccm and RF power is set as about 450 W. A surface nitridation step is then carried out for about 5 minutes at around 700° C. The substrate temperature is then raised to about 850-900° C. High density AlN islands growth is carried out for about 5-10 minutes. Then GaN nanocolumns are grown under the same temperature for around another two hours. GaN nanocolumns produced in this manner are typically found to have diameters of −90 nm and heights of −800 nm.
Here, the HVPE epitaxial lateral overgrowth process described in Example 1 is replaced by a time-modulated HVPE growth method. In this method, the flow sequence of reagent gases is on (NH3 and GaCl on) and off (GaCl and NH3 off, HCl on) in turn for the growth mode and the etching mode respectively. The time for the on and off period is set to be around 3 minutes and 1 minute respectively. The HCl flow during the etching is set at 80 sccm. The GaN growth step is continued until a GaN epitaxial layer of sufficient thickness is produced. For the growth with the V/III ratio set between 10 and 40 in the vertical reactor of
Here, the HVPE epitaxial lateral overgrowth process described in Example 5 is replaced by a modified time-modulated HVPE growth. The growth is divided into etch, annealing, enhanced lateral growth and normal growth stages. In this example the flow of reagent gases for the etch stage is GaCl and NH3 off, HCl on with gas flow of 80 sccm. For the annealing stage the flow is GaCl and HCl off, NH3 on. For the enhanced lateral growth stage the flow is GaCl and NH3 on, HCl on with gas flow of 5 sccm, total H2 flow increases from 60 to 200 sccm. Finally, for the normal growth stage the flow is GaCl and NH3 on, HCl on with gas flow of 5 sccm, total H2 flow of 60 sccm. The time for the etch, annealing, enhanced lateral growth and normal growth periods is set to be 1, 1, 3 and 2 minutes respectively.
Here, the nanocolumn HVPE growth process described in Example 1 is modified by doping the GaN with silane (2% in H2) with gas flow from 2 to 20 sccm for n-GaN nanocolumns.
Here, the nanocolumn HVPE growth process described in Example 1 is modified by adding an extra p-type GaN layer in the final stage of nanocolumn growth. The p-GaN is doped with Mg using Cp2Mg or Magnesium vapour injected through gas inlet 8 with a flow of around 7 to 50 sccm (Cp2Mg bubbler pressure 1000 mbar, bubbler temperature 25° C., carrier gas H2).
In this Example, the thick GaN grown in Example 1, being n-type doped with a modified p-GaN top layer of the nanocolumns as produced in Example 8, is separated from the substrate using an electrochemical method. The thick n-GaN acts as the anode, a Pt mesh is used as the cathode and either KOH or H3PO4 is used as the electrolyte. A bias voltage (to Pt reference electrode) of about 3.5 to 4 V is applied to selectively etch away the p-GaN. The thick n-GaN is typically separated from the substrate after 30 minutes etching.
It will be apparent to those skilled in the art that a wide range of methods and process parameters can be accommodated within the scope of the invention, not just those explicitly described above. For example, nanostructure growth may be initiated in a variety of ways, which will be apparent to those skilled in the art. The nanostructures may be grown so as to have various shapes of tips, chosen as appropriate for the application in hand. The material of the nanostructure does not have to be constant, for example the alloy content may be varied along its height so that its properties are most suitable for the specific application. For example, the alloy content may be selected so as to optimise absorption during a laser ablation separation process. Alternatively, a change in the alloy content may optimise the lattice constant for the overgrown semiconductor. Furthermore, the nanostructure material need not be identical to that of the overgrown compound semiconductor.
In the specific examples described, nanostructures are grown onto the substrate before overgrowth of the compound semiconductor material. However, use of a nanostructure layer may permit relatively easy removal of the semiconductor, without causing undue damage to the underlying nanostructures. In this case, the substrate and nanostructure formation may be re-used in a subsequent process in accordance with the invention. In other words, a substrate with its nanostructures may be used more than once or even repeatedly as a base for the overgrowth of compound semiconductor materials. This would have significant cost savings for the second and each subsequent overgrowth.
| Number | Date | Country | Kind |
|---|---|---|---|
| 0605838.2 | Mar 2006 | GB | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/GB07/01011 | 3/19/2007 | WO | 00 | 9/9/2008 |
