United States

Introduction: Titanium Dioxide (TiO2) is a semiconductor that can be found under Brookite, Rutile and Anatase phases, where the former has gained relevance due to its photocatalytic features, high chemical stability, low toxicity/cost, and strong oxidizing capacity under UV light [1]. Exposing TiO2 to UV light leads to the production of indirect electronical transition that enables the formation of reactive species, with free radical hydroxyl (HO) and superoxide (O2) that promotes decomposition of organic contaminants [2]. Two techniques will be compared. Atomic Layer Deposition (ALD) is physical and requires two vapor precursors injections inside a chamber separated by the purge of an inert gas, and each precursor saturates the surface of the substrate leading to the formation of the TiO2 thin film. Hence, the ALD methodology is considered a stepped self-limiting technic [3], where the thickness of the thin film relies on the number of deposited cycles under half vacuum pressure conditions (0.1 torr). Sol-Gel is a chemical technique applied at room temperature and atmospheric pressure conditions, where simultaneous reactions are produced: hydrolysis and condensation [4]. Initially, the hydrolysis requires a metallic precursor (titanium alkoxide), solvents and acidification of the solution, which results in the formation of Titanium Hydroxides and the condensation process finally leads to the Titanium Dioxide synthesis [5]. In this work, TiO2 thin films are generated over glass substrates previously cleaned through DI water, 2propanol and acetone. For ALD the Titanium Alkoxide Tetraisopropyl Orthotitanate (Ti[OCH(CH3)2]4) was taken as precursor, and vaporized water for the formation of TiO2; under a Ni atmosphere at 20 sccm, with 1100 cycles (20 nm thick), a working temperature fixed at 200 C and pressure of 2.45x10-1 torr. For Sol-Gel, the solution was also prepared using Ti[OCH(CH3)2]4, but with ethanol (CH3CH2OH), acetic acid (CH3COOH), H2O2 and DI water, as explored in [5-7]. Solution is spin coated over hydrolyzing substrate (H2SO4 + H2O2 in 3:1 concentration. Manufactured films from both techniques, were taken to an annealing process at 450 C and 550 C, under a Ni atmosphere with a gas flux of 4000 sccm during 1 hour. The characterization of TiO2 thin films was realized before and after the annealing process, starting from X-Ray Diffraction (XRD) to the crystallin phase of the TiO2 anatase on each treatment, in order to measure the intensity of the phase in the plane (101) with an angle of 25.16±0.2° (Fig. 1) [2]. Also, the absorption spectrum was measured using the Lambert-Beer Law [8] and the bandgap energy by direct gap of the semiconductor was estimated as a function of temperature (Fig. 2); moreover, the morphology of the films surface was observed with the Scanning Eletron Microscopy (SEM) technique and the elemental analysis of the films by energy dispersive X-ray spectroscopy (EDX). Finally, the resistivity was measured using the Van der Pauw 4-point technique and the charge mobility was analyzed with Hall effect (Fig. 2). References [1] A. Ibrahim, W. Phoohinkong, W. Mekprasart, and W. Pecharapa, Mater. Today Proc., vol. 5, no. 5, pp. 10903–10909, 2018. [2] R. Katal, S. Masudy-Panah, M. Tanhaei, M. H. D. A. Farahani, and H. Jiangyong, Chem. Eng. J., vol. 384, no. October 2019, p. 123384, 2020. [3] V. Pore, A. Rahtu, M. Leskelä, M. Ritala, T. Sajavaara, and J. Keinonen, Chem. Vap. Depos., vol. 10, no. 3, pp. 143–148, 2004 [4] Brinker C. Jeffrey, p. 462, 1990. [5] M. B. Tahir, K. Nadeem, M. Hafeez, and S. Firdous, Indian J. Pure Appl. Phys., vol. 55, no. 10, pp. 716–721, 2017. [6] M. Urbonavicius, S. Varnagiris, S. Sakalauskaite, E. Demikyte, S. Tuckute, and M. Lelis, Catalysts, vol. 11, no. 7, 2021. [7] C. Villanueva Jaramillo, A. M. Pedroza, J. C. Salcedo, A. K. Carrascal Camacho, and A. E. Florido Cuellar, pp. 1–125, 2011. [8] G. L. Tian, H. B. He, and J. Da Shao, Chinese Phys. Lett., vol. 22, no. 7, pp. 1787–1789, 2005.

EMC 2023

Atomic Layer Deposition (ALD) and Sol-Gel Techniques Comparison from the Perspective of TiO2 Thin-Films Fabrication

sol-gel

photocatalysis

tio2

The 65th Annual Conference on Magnetism and Magnetic Materials (MMM 2020) was held in a virtual form. The COVID-19 pandemic, with its associated uncertainty about international travel and the ability to gather in large groups, meant that the Steering Committee decided to cancel the face-to-face meeting that had been planned in Palm Beach, Florida November 2-6, 2020.

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MMM 2020

technical paper

The Electronic Materials Conference (EMC) is the premier annual forum on the preparation, characterization and use of electronic materials. This year’s event will feature a plenary session, topical sessions, a poster session and more.

EMC is coordinated with the Device Research Conference (DRC). This recognizes the strong interaction between device and electronic materials research and provides fruitful exchange of information between attendees of both Conferences.

The Electronic Materials Conference (EMC) is the premier annual forum on the preparation, characterization and use of electronic materials. 

Self-aligned channel regions in thin-film transistors (TFTs) have advantages in reduced parasitic capacitance and stage delay, and a reduction in overhead real estate. A common method used to fabricate self-aligned a-Si:H TFTs is to utilize a through-glass exposure of photoresist which is blocked by the opaque metal bottom-gate electrode [1,2]. This process does not require an additional photomask or lithographic alignment, and thus supports low production cost. Sputtered IGZO has been introduced into flat panel display product manufacturing, exhibiting a channel mobility of approximately an order of magnitude higher than a-Si:H. The working source/drain electrodes in IGZO TFTs can be direct metal contact regions to the IGZO, without the need for additional processes such as doping to render the IGZO conductive. Proper metallurgy and annealing processes can provide ohmic behavior with minimal series resistance, however this usually requires several microns of gate-to-source/drain overlap to ensure such behavior. This work provides an interpretation of donor activation in self-aligned bottom-gate IGZO TFTs with ion-implantation of boron (11B+) and phosphorus (31P+) species as the source/drain treatment. In previous investigations of boron implantation, utilizing an anneal-implant sequence resulted in self-aligned devices with transfer characteristics comparable to non-self-aligned TFTs. A left shift in transfer characteristics was observed following thermal stress at 175 °C which is not consistent with recent work from alternate sources which have shown boron implanted devices temperature stable at 200 °C [3,4]. It is hypothesized that this is the result of implant species contamination due to the presence of hydrogen in the implant gas distribution system. In contrast, following an implant-anneal sequence at 400 °C did not support an electrically active species. The implant-anneal strategy seems to result in a different bonding arrangement which does not support donor-like behavior related to boron. Self-aligned phosphorus implants present promising behavior using the implant-anneal strategy, potentially serving as a lightly doped drain (LDD) structure for sub-micron scaled devices.

Donor Activation in Boron and Phosphorus Implanted Self-Aligned Bottom-Gate IGZO TFTs

We report the successful fabrication and characterization of thin film transistors (TFTs) with a significant ~95.7% reduction on the saturation currents thanks to ultraviolet ozone (UVO) and controlled annealing treatments. Such TFTs (Figure 1) were designed for autonomous microrobotic applications. On this specific study we exposed the TFTs to a 3 min ultraviolet ozone (UVO) with 184.5 nm (17%) and 253.7 nm (83%) UV light emissions at a constant light intensity (28-32 mW cm−2), together with 1 hour annealing treatment at 300 °C to yield contact resistance of 74.5±1.16 Ω and sheet resistance of 5.376 Ω/square. Although, defects and uniformity of materials usually affect the performance of TFTs such as threshold voltage, contact resistance, and output current [4,5], the consistent reduction of saturation currents (~252 μA @ Vg=50 V) obtained after UVO treatment (Figure 2) are evidence that oxygen vacancies were reduced, and metal-oxygen bonding were increased. TFT are versatile semiconductor devices with wide applications, ranging from liquid crystal displays to flexible and transparent electronic devices [1-3] expected to have low drain-source currents during saturation to reduce de energy consumption, especially critical in autonomous small scale robotic applications. The proposed TFTs were fabricated over insulated (100 nm SiO2) P-type (100) silicon substrate with bottom-gate/top-contact architecture. The device cross section shown in Figure 1a, contains 50 nm semiconductor layer of amorphous Indium-gallium-zinc oxide (InGaZnO4) via sputtering; 10 nm/50 nm Cr/Au electrode layers deposited by electron beam evaporation for drain, source and gate; and 10 nm of Al2O3 grown via atomic layer deposition as dielectric. We also designed and array of TFTs with different sizes (channel with and length) and test features, to extract important parameters for compact modeling. Lengths ranges between 8 µm to 160 μm and widths between 10 µm to 1000 μm. Test features include transfer length method (TLM), capacitance extraction, and four-point van der Pauw for hall probe measurements to extract mobility. The fully fabricated chip and TFT are shown in Figure 1b-1c. I-V curves were measured for all channel dimensions and saturation currents are summarized in Figure 3. As expected, the saturation current decreases with the length and increases with TFTs width, useful relationships that provide reference for designing specific power on future TFTs generations with improved performance after UVO and annealing technique. Acknowledgement: The authors would like to thank the support from the Mechanical and Aerospace Engineering Department. University of California, Irvine. References: [1] Hays, D. C., Gila, B. P., Pearton, S. J., & Ren, F. (2017). Energy band offsets of dielectrics on InGaZnO4. Applied Physics Reviews, 4(2), 021301. [2] Zhou, X., Cao, H., Zhou, Z., Cao, J., & Yu, J. (2017). Structural, electrical and optical properties of InGaZnO4InGaZnO4 and In29Sn3O48In29Sn3O48: a first-principles study. Journal of Computational Electronics, 16(2), 280-286. [3] Nomura, K., Takagi, A., Kamiya, T., Ohta, H., Hirano, M., & Hosono, H. (2006). Amorphous oxide semiconductors for high-performance flexible thin-film transistors. Japanese journal of applied physics, 45(5S), 4303. [4] McDonnell, S., Addou, R., Buie, C., Wallace, R. M., & Hinkle, C. L. (2014). Defect-dominated doping and contact resistance in MoS2. ACS nano, 8(3), 2880-2888. [5] Suemori, K., Uemura, S., Yoshida, M., Hoshino, S., Takada, N., Kodzasa, T., & Kamata, T. (2008). Influence of fine roughness of insulator surface on threshold voltage stability of organic field-effect transistors. Applied Physics Letters, 93(3), 264.

Improved Electrical Performance of InGaZnO4 Thin-Film Transistors with UV Ozone Treatment

Two-dimensional (2D) van der Waals transparent conducting metal oxides (TCOs) have recently emerged as a promising platform for fabricating flexible optoelectronic devices, offering high mobility, high transparency, and improved mechanical flexibility. This class of 2D oxides can be synthesized at low temperatures (< 180 °C) without vacuum by utilizing the unique physics of liquid metal surface oxides. Here we report continuous liquid metal printing for scalable fabrication of high-performance 2D TCOs compatible with polymer substrates. We apply a spontaneous Cabrera Mott growth at low-temperatures afforded by the low melting point of In, Ga, Sn, and their alloys. In our continuous liquid metal printing (CLMP) method, these metal droplets serve as the source material for simultaneously growing and depositing these films via adhesion of the 2-3 nm thick solid oxide skin over large areas (~ 100 cm2). The high speed of this roller-based deposition method (> 6 meters/minute) is also particularly promising because Cabrera Mott synthesis naturally yields high conductivity, sub-stoichiometric oxides via their oxidation from the metallic phase. This allows the use of a rapid process, eliminating thermal post-annealing steps otherwise necessary for low-temperature metal oxides, opening up greater opportunities for utilizing lower cost plastic substrates. In this presentation, we demonstrate a new class of layered TCO heterostructures exploiting modulation doping interactions between 2D InOx and 2D GaOx. We characterize the crystallinity of these 2D oxide films as a function of deposition temperature within the range of plastic substrates (160 °C to 240 °C) by XRD and apply TEM to observe the large plate-like cubic InOx grain structure. These overlapped grain morphologies lead to high conductivity (up to 600 S/cm) despite the exceptionally low total processing time (3s per layer) and low temperatures (180 °C). Through XPS, UV-Vis, and Hall characterization, we examine the modulation doping effect induced by the InOx / GaOx interface in these multilayer TCOs. UV-Vis absorption spectroscopy reveals the impact that modulation doping can enhance visible range transparency through a Burstein Moss effect-induced optical bandgap widening. We characterize the flexibility of these 2D TCOs in comparison with sputtered ITO electrodes on plastic substrates, showing how the ultrathin nature provides substantially greater strain tolerance under cyclic bending. These results show how interfacial modulation doping interactions can be used to control and enhance the electronic properties of 2D oxides beyond the state of the art for low-temperature processed metal oxides.

Continuous Liquid Metal Printing of High-Performance 2D Oxide Heterostructures

In this study, we demonstrate the utility of impurity band conduction in overcoming the limitations of conventional p-type doping in Al-rich aluminum gallium nitride (AlGaN). First, a model is developed to understand the impurity band conduction mechanism in Mg-doped AlGaN. It is hypothesized that at high Mg doping concentrations (mid-1019 cm-3) -below the Mott transition-, the overlap of the Mg dopant states can cause the dopant energy level to split into a quasi-continuous impurity band. This provides an alternate route for conduction, where the carriers can propagate through the impurity band with a much-reduced activation energy as compared to the relatively large Mg ionization energy required for the valence band transport. It is worthwhile to note that the presence of compensating point defects can disrupt the overlap of the Mg orbitals and, hence, impede the formation of the impurity band. Mg-doped Al-rich AlGaN epilayers were grown on sapphire and single-crystal AlN substrates by metalorganic chemical vapor deposition. In accordance with the model, relatively heavy Mg doping in conjunction with compensation control was found to be critical to induce the impurity band formation. Record-low p-type resistivities of 9.7 and 37 Ωcm were achieved in Al0.7Ga0.3N and Al0.8Ga0.2N films grown on the native substrate. The resistivity exhibited shallow activation energy of ~30 meV for a wide temperature range of 150-500K. Valence band conduction associated with a large Mg ionization energy was observed to dominate above 500K. Interestingly, the Hall coefficient data was found to deviate from classical semiconductor physics. The apparently anomalous results were attributed to the fact that the Hall effect associated with the carriers propagating in the impurity band differs qualitatively from the quasi-free motion of holes in the valence band leading to a fundamentally different Hall scattering factor. This work demonstrates the utility of impurity band conduction to achieve technologically relevant p-type conductivity in Al-rich AlGaN. Al-rich AlGaN devices are poised to enable a host of optoelectronic applications owing to their desired properties such as low size, weight, and potential operating power. While Si doping has been demonstrated to be effective in achieving n-type Al-rich AlGaN films, efficient p-type doping remains a significant challenge. Mg, the most explored p-type dopant in AlGaN presents a rather high ionization energy of >400 meV. This creates a fundamental bottleneck as only a small fraction of the Mg atoms ionizes at room temperature to generate free holes. This results in a high resistivity >100 Ωcm in Mg-doped Al-rich AlGaN grown via the conventional Mg doping approach. While alternate doping approaches such as short-period superlattices, composition modulation, and Mg delta doping allow for low lateral resistivity in p-AlGaN the vertical conduction is limited due to the barriers associated with the periodic oscillation of the energy bands. The polarization-graded AlGaN approach, on the other hand, necessitates the grading toward Ga-rich compositions to achieve high hole concentration and to favor the Ohmic contact formation. This approach suffers from UV-C absorption loss in the p-type layer, significantly decreasing the light extraction efficiency in optoelectronic devices. Therefore, it is of significance to devise techniques for achieving low p-type resistivity in Al-rich AlGaN without modulating the composition or the doping profile.

Achieving Technologically Relevant P-Type Conductivity in Al-Rich (>70% Al) AlGaN Using Impurity Band Conduction

Recently, beryllium has regained attention as a potential p-type dopant in III-Nitrides due to its shallower acceptor level than magnesium. We recently reported the first systematic investigation of GaN:Be grown using metal-organic chemical vapor deposition (MOCVD) [1]. Despite the successful incorporation of Be into GaN grown by MOCVD, conductive p-type GaN:Be has yet to be realized. This may be in part due to poor incorporation efficiency of Be under normal growth conditions where [Be] saturates at about 1–5×1018 cm-3. Techniques to increase [Be] such as using a pulsed growth method have been successful, but result in material degradation and p-type conductivity was still not achieved. Furthermore, a prominent YLBe band in photoluminescence studies indicates the presence of a deep donor, which may be responsible for the compensation of activated Be. Co-doping GaN with Be and Mg has been suggested as a possible way to increase Be incorporation and suppress YLBe, and initial studies using MBE-grown GaN:Be+Mg showed promise [2,3]. However, no comprehensive studies were performed, and this technique has never been attempted using MOCVD. Because Be and Mg induce local tensile and compressive strains, respectively, due to their atomic sizes relative to Ga, co-doping may improve solid solubility of both species and encourage incorporation of acceptors into electrically active Ga sites. In this work, we investigate the effects of Be+Mg co-doping in GaN. Several different doping conditions are studied, including Be+Mg continuous co-coping and layered Be and Mg doped layers. The effects of co-doping on Be and Mg incorporation, material quality, activation efficiency, and conductivity are discussed and compared to the results of singly doped GaN. [1] B. McEwen, et al., MOCVD Growth and Characterization of Be-Doped GaN. ACS Appl. Electron. Mater., 4(8), 3780-3785 (2023). [2] F. B. Naranjo, et al., Study of the Effects of Mg and Be Co-Doping in GaN Layers. Phys. Stat. Sol. (a), 180(1), 97-102 (2000). [3] A. Kawaharazuka, Be and Mg co-doping in GaN. J. Cryst Growth, 301, 414-416 (2007).

MOCVD GaN Co-Doped with Mg and Be

The performance potential of ideal infrared detectors is fundamentally limited by the thermally generated diffusion and depletion dark currents of the infrared absorbing layer due to its narrow energy gap and consequently large intrinsic carrier concentration. Dark current manifests as shot noise in the detector, which leads to a decrease in sensitivity as the square root of the magnitude of the dark current. Although decreasing the operating temperature is an effective strategy to reduce dark current, active cooling of the device increases system size, weight, and power, which is not tolerable for certain applications. An alternative strategy, utilized to great effect in the nBn infrared detector architecture, is to hinder the formation of depletion regions in the narrow-gap material and thereby eliminate the depletion current. This can greatly reduce the total dark current as depletion current is proportional to intrinsic carrier concentration, whereas diffusion current is proportional to the equilibrium minority carrier concentration. Unfortunately, despite the ability to minimize the equilibrium minority carrier concentration by increasing the doping concentration, inclusion of donor impurities also increases the Shockley-Read-Hall and Auger recombination mechanisms, which in turn increases diffusion dark current, limiting its reduction via doping. Furthermore, reduction of the minority carrier lifetime decreases the diffusion partial quantum efficiency, which also degrades detector sensitivity. Therefore, a complex trade-off exists between doping density’s effects on dark current and minority carrier lifetime which can be balanced to achieve an optimum detector sensitivity. Here, an investigation on the effects of material parameters on minimal attainable shot noise-limited noise equivalent irradiance is performed using models of diffusion current density as well as diffusion partial quantum efficiency derived from carrier continuity equations. The model is then verified using Silvaco TCAD simulations of nBn devices. Additionally, two mid-wave infrared InGaAs/InAsSb superlattice nBn detectors grown with different absorber doping densities are characterized and compared to the model results.

Sensitivity Optimization in Diffusion-Limited Infrared Detectors

β-gallium oxide (β-Ga2O3) is of intense current interest because of its ultra-wide bandgap, high critical field, and availability of melt-grown substrates. Point defects and complexes determine the properties of bulk crystals as well as epitaxial layers, thus, predictive models of defect concentrations under various impurity and processing scenarios are of very high value. First-principle calculations of defect energetics have provided critical insights into the defect system in β-Ga2O3, but translating computed enthalpies into defect concentrations corresponding to real-world crystal growth requires additional steps. Growth or annealing experiments typically control the sample trajectory in terms of temperatures and partial pressures, while computation papers frequently present results holding chemical potentials constant. Here we report our quantitative modelling of equilibrium defect concentrations in Ga2O3, taking into account especially the temperature dependence of the bandgap and temperature-dependent chemical potentials from the Ga-O system’s known thermochemistry. Additionally, we compute results for realistic sample types such as Fe- or Sn-doped wafers accounting for the fixed concentrations of these impurities as opposed to their fixed chemical potentials. Results are presented for various background n-type doping and for equilibrium and quenching, corresponding respectively to 0 or infinite cooling rates. We find significant departures from prior simpler predictions, especially in the case of the bandgap temperature dependence. We compare our predicted results to empirically-known cases, such as annealing in O2 or Ga2O vapors. Finally, to give semi-quantitative insight into defect concentrations expected in finite-sized samples subjected to finite cooling rates without full-fledged multidimensional defect reaction-diffusion simulations, we introduce the concept of generalized quenching as a 3rd type of computation. At the heart of generalized quenching is the insight that, because of their different diffusion constants, different types of defects located at different distances from free surfaces will be “frozen-in” at different temperatures. Essentially by combining equilibrium and quenching calculations, it is thus possible to predict the defect concentrations present following cooling as a function of radius within a boule or within thin films of different thicknesses. We compare these results to the known phenomena from bulk crystal growth, indicating differences in carrier density between the center and periphery of CZ-grown boules.

Temperature-Dependent Calculations of β-Ga2O3 Defect Concentrations for Equilibrium, Full Quenching and Generalized Quenching Scenarios

Gallium oxide (Ga2O3), an emerging ultra-wide bandgap semiconductor material with a bandgap ~ 4.8 eV, occurs in the trigonal , monoclinic , cubic and orthorhombic polymorphs. The thermodynamic stable phase of β-Ga2O3 has been the primary focus for future power electronic devices due to the availability of semi-insulating to n-type doped free-standing substrates. Although γ-Ga2O3 has been identified as the least stable phase, γ-Ga2O3 inclusions have been found in many β-Ga2O3 films, particularly when Al or Mg is present. 1–3 These γ-phase inclusions are recognized as a potential problem for devices based on β-Ga2O3.1 In this study, Ga2O3 films were deposited on (100) MgAl2O4 in the temperature range of 550 °C to 850 °C via metal-organic chemical vapor deposition (MOCVD). Post-deposition thermal treatments were conducted in air at temperatures between 800 °C to 1000 °C. The phase composition and nanostructure of the as-grown and annealed films were investigated using X-ray diffraction and transmission electron microscopy (TEM). Phase-pure β-Ga2O3 was observed in the films deposited at 550°C and 650 °C, whereas γ-Ga2O3 -based solid solutions (hereafter referred to as γ-phase) were formed at 850°C, and a mixture of β-Ga2O3 and γ-phase were observed in the films grown at 750°C. The transformation of β-Ga2O3 to γ-phase originated at the film/substrate interface and was accompanied by interdiffusion of Al and Mg from the substrate. The minimum atomic percent of Al + Mg associated with the phase transformation was determined to be ~ 4.6 at%. Atomic scale TEM characterization indicates that Al and Mg have a strong preference for octahedral sites whereas Ga prefers the tetrahedral sites, to form an inverse spinel structure. It is postulated that the octahedral site preference of Al and Mg drives the β-Ga2O3 to γ-phase transition and, as a result, enhances the observed thermal stability of the γ-phase at elevated temperatures. 1 C.S. Chang, N. Tanen, V. Protasenko, T.J. Asel, S. Mou, H.G. Xing, D. Jena, and D.A. Muller, APL Mater. 9, (2021). 2 A.F.M.A.U. Bhuiyan, Z. Feng, J.M. Johnson, H.L. Huang, J. Sarker, M. Zhu, M.R. Karim, B. Mazumder, J. Hwang, and H. Zhao, APL Mater. 8, (2020). 3 Q. Hou, K. Liu, X. Chen, J. Yang, Q. Ai, Z. Cheng, Y. Zhu, B. Li, L. Liu, and D. Shen, Physica Status Solidi - Rapid Research Letters 16, (2022).

Phase Transformation of β-Ga2O3 to Ga2O3 -Based γ-Phase Spinels on (100) MgAl2O4 Substrate

Gallium oxide (Ga2O3) is a conducting transparent semiconducting oxide and ultra-wide bandgap material which allows for a large critical electric field that maximizes frequency and voltage operation. Due to its large Baliga’s figure of merit (3200 * Si) and inexpensive melt-growth methods, Ga2O3 is of interest in electrical and optical applications [1, 2, 3]. β-Ga2O3 is the most chemically and thermally stable phase with an anisotropic bandgap between 4.5 and 4.9 eV, depending on orientation [1, 2, 3]. To control the electrical and optical properties of Ga2O3 and aluminum gallium oxide alloy (AGO) within devices, understanding where their defects come from and how they develop is important. For example, although point defects can be used to control their properties, e.g. doping, extended defects tend to negatively impact their operation. As such, identifying the types of defects caused by growth or fabrication processes is important for developing those processes and reducing undesirable defects. One method to characterize defects is through photoluminescence (PL) which is a noninvasive process. For β-Ga2O3, the PL spectrum is broad over the UV, blue, and green wavelengths making deconvolving the spectra extremely difficult [1, 2]. There have been studies in the literature to determine the origin of the β-Ga2O3 spectra, but those studies typically focus on point defects as a cause [1]. Here, the correlation between sample quality and extended defects is possible with PL and PL Microscopy (PLM). Comparing β-Ga2O3 or AGO films and bulk samples shows that extended defects have an essential role in the PL emission. Homogeneous films with no extended defects and bulk crystals will yield a UV dominant PL emission. Samples of poor film quality that have extended defects throughout will have a dominant blue PL emission. This means the quality of a sample, in terms of the density or extended defects, can be determined through PL [1]. Furthermore, sample topography and extended defects can be identified through PLM [2]. Single crystal samples have uniform UV emission. That said, any topography can alter the emission intensity due to refraction and diffraction. Furthermore, any topography that is altered due to defects also causes a contrast in emission intensity. As such, PLM tends to match AFM and SEM images. But, there are cases where PLM can diverge from AFM and SEM due to other extended defects within the film, which are more luminescent than surface defects/topography. Some defects identified using PLM include cracks running along [001] on AGO films, rotational domains found in β-Ga2O3 grown on sapphire, incoherent stacking faults from (-201) β-Ga2O3 grown on Fe-doped β-Ga2O3, and sympetalous defects which are a newly discovered defect [2]. The sympetalous defect is found on metalorganic vapor-phase epitaxy (MOVPE) films grown on (010) Ga2O3. This defect generally grows out from underlying line defects in the substrate, such as nano-pipes, which is similar to v-defects found in GaN. The defect creates a polycrystalline region in the film, expanding out from the initial starting line defect seed [3]. PL shows that the sympetalous defects are polarization-dependent. Furthermore, circular polarization also shows luminescence likely caused by the defect grains having a semi-helix growth with themselves and/or bulk crystal surrounding the defect [3]. Lastly, the quality of a sample can be determined by looking at the density and surface size range of defects on the surface of a sample. Sympetalous defects are similar in size and have the same density as substrate etch-pits. Nodular defects, on the other hand, have a wide variety of sizes and density that increases with thickness [3]. [1] J. Cooke, et al., Scientific Reports, 12, 3243 (2022). [2] J. Cooke, et al., Optical Material Express, 12 (11), 4341 (2022). [3] J. Cooke, et al., J. Vac. Sci. Technol. A, 41 (1), 013406 (2023).

Characterization Analysis of Extended Defects in β-Ga2O3 and AGO

Gallium oxide (Ga2O3) has an extremely wide bandgap, predicted high breakdown field, and can be produced from melt crystal growth techniques making it attractive for next-generation high-power electronics. It is well-known that the optical transitions in monoclinic β-Ga2O3 are anisotropic; the threshold energies for carrier generation using linearly polarized light depend on crystallographic direction. Using transmission optical spectroscopy, which probes subtly differently than e.g. ellipsometry, we have investigated the optical transitions of Fe doped [100] β-Ga2O3 as function of elevated temperature and have documented the dramatic bandgap narrowing with temperature which was recently explained using density functional theory [1]. Here we also report on the anisotropy and doping dependencies of the disorder-induced Urbach tails in the optical absorption coefficient for β-Ga2O3. Band tails in semiconductors depend on both static disorder and the dynamic disorder induced by phonons mediated by the electron-phonon coupling. Given the low symmetry of β-Ga2O3 and its strong electron-phonon coupling, we predicted that the Urbach tails should also exhibit significant anisotropy. We show that this is indeed the case, and also provide results for UID- and Fe-doped crystals both of which exhibit larger band tails as expected. References [1]. Lee, C., Rock, N.D., Islam, A., Scarpulla, M.A. and Ertekin, E., 2023. Electron–phonon effects and temperature-dependence of the electronic structure of monoclinic β-Ga2O3. APL Materials, 11(1), p.011106.

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Donor Activation in Boron and Phosphorus Implanted Self-Aligned Bottom-Gate IGZO TFTs

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