United States

The 2D TMD-based thin film materials have been believed to be a potential candidate for replacing the Si CMOS technology. Ideally, the 2D material has better device scaling and interface properties. However, contact resistance has been a big issue in the transistor&#39;s design due to the difficulties in material doping. It is difficult to dope in 2D material in the contact region to reduce the contact resistance and form an ohmic contact. Hence, most of the work is to find a good metal to adjust the work function. For nMOSFET, a smaller work function material is needed, and a high work function metal is needed for p-MOS. In this work, a new CFET design based on 2D Janus MoSSe material has been proposed based on the polarization field induced by the asymmetric structure. The 2D Janus MoSSe material has been found to have a strong polarization field, which is even larger than the nitride-based polar material because the structure is asymmetric. The p-type and n-type ohmic contact can be formed at the opposite surface by utilizing the asymmetry polarization property of the two opposite surfaces. The positive polar charge surface will attract electrons to form a 2DEG at the surface and make the n-type ohmic contact. The negative polar charge surface will attract holes to form a 2DHG and a p-type ohmic contact. Based on these properties, the n- and p-FET can be produced without doping; combined into a CFET by symmetric structure. In our DFT calculation, the dipole fields are up to 106 V/cm order (Table 1) for both MoSSe and WSSe. The DFT calculated projected band structures of 1 and 2-layer-MoSSe/graphene systems with different side contact are calculated to show the p- and n-type contact formation (Fig.1). If graphene makes contact with the Se-side, the 0.2 eV N-type Schottky barrier is formed. And yet, if graphene makes contact with the S-side, we see a 0.3 eV P-type Schottky barrier. In the 2-layer MoSSe case, we find that the N-type barrier for S-side contact is reduced to 0.1 eV, and the Se-side achieves p-type ohmic contact. The intrinsic dipole-induced p- and n-type ohmic contact can also be formed at the metal/MoSSe interface. The DFT extracted data, such as spontaneous polarization and thickness, are further put into the 2D finite difference Poission-Schrödinger solver developed by our lab to design the transistor. Similar to the GaN HEMT devices, this intrinsic dipole in MoSSe material causes band bending, producing 2DEG and 2DHG at the interface region (Fig.2). Thus, the p-FET and n-FET structures are constructed by placing a channel region between two Metal/MoSSe interfaces through attaching contacts to the different faces of JTMD. Then combining p- and n-FET, the CFET structure can be fabricated using a single film. Based on the above-mentioned property, we design the p- and n-FET structure shown in Fig.3 and Fig. 4 and perform the simulation. The double gate structures are used to have better control of the channel. To make the enhanced mode of operation, the HfO2 material was chosen as the gate dielectrics. The device achieves a smaller SS value (~61 mV/dec) (Fig.5 and Fig. 6). Fig. 7 is the majority carrier density plot with different gate biases, the switching between on and off states can be observed. Furthermore, to make the device fabrication process realistic, we proposed a structure that could be built layer by layer (Fig.8). Based on the I-V curve obtained from the 2D simulation result, we built the model and further performed the circuit simulation by LTspice (Fig.9). Set VDD equals to 1.5V, and the middle plot is Vin to Vout of the CMOS inverter. The JTMD materials have a similar transport property as MoS2 and WS2. With the built-in polarization field and a proper design, it is possible to make CFET devices in a single thin film without doping.

EMC 2023

Surface Polarization Engineering Design of 2D Janus MoSSe Complementary Field Effect Transistors

cfet

spontaniuos polarization

2d material

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), which will be held during the same week, from June 20-23. This recognizes the strong interaction between device and electronic materials research and provides fruitful exchange of information between attendees of both Conferences.

![](https://assets.underline.io/uploads/markdown_image/1/image/eb26c24a18d5d1030616afa4f993cf89.png)
	
<a href="https://www.mrs.org/docs/default-source/meetings-events/mrs-conference-services/2021/emc-2021/2021-emc-program-at-a-glance-6-16-21.pdf?sfvrsn=e39f950c_4">Latest Program-at-a-Glance</a>

<a href="https://drive.google.com/file/d/1eiS1ao4p83VNy8xgHs3Rls7gTQjx7Rc4/view?usp=sharing">Full Program with Abstracts</a>

EMC 2021

The 2D TMD-based thin film materials have been believed to be a potential candidate for replacing the Si CMOS technology. Ideally, the 2D material has better device scaling and interface properties. However, contact resistance has been a big issue in the transistor's design due to the difficulties in material doping. It is difficult to dope in 2D material in the contact region to reduce the contact resistance and form an ohmic contact. Hence, most of the work is to find a good metal to adjust the work function. For nMOSFET, a smaller work function material is needed, and a high work function metal is needed for p-MOS. In this work, a new CFET design based on 2D Janus MoSSe material has been proposed based on the polarization field induced by the asymmetric structure. The 2D Janus MoSSe material has been found to have a strong polarization field, which is even larger than the nitride-based polar material because the structure is asymmetric. The p-type and n-type ohmic contact can be formed at the opposite surface by utilizing the asymmetry polarization property of the two opposite surfaces. The positive polar charge surface will attract electrons to form a 2DEG at the surface and make the n-type ohmic contact. The negative polar charge surface will attract holes to form a 2DHG and a p-type ohmic contact. Based on these properties, the n- and p-FET can be produced without doping; combined into a CFET by symmetric structure. In our DFT calculation, the dipole fields are up to 106 V/cm order (Table 1) for both MoSSe and WSSe. The DFT calculated projected band structures of 1 and 2-layer-MoSSe/graphene systems with different side contact are calculated to show the p- and n-type contact formation (Fig.1). If graphene makes contact with the Se-side, the 0.2 eV N-type Schottky barrier is formed. And yet, if graphene makes contact with the S-side, we see a 0.3 eV P-type Schottky barrier. In the 2-layer MoSSe case, we find that the N-type barrier for S-side contact is reduced to 0.1 eV, and the Se-side achieves p-type ohmic contact. The intrinsic dipole-induced p- and n-type ohmic contact can also be formed at the metal/MoSSe interface. The DFT extracted data, such as spontaneous polarization and thickness, are further put into the 2D finite difference Poission-Schrödinger solver developed by our lab to design the transistor. Similar to the GaN HEMT devices, this intrinsic dipole in MoSSe material causes band bending, producing 2DEG and 2DHG at the interface region (Fig.2). Thus, the p-FET and n-FET structures are constructed by placing a channel region between two Metal/MoSSe interfaces through attaching contacts to the different faces of JTMD. Then combining p- and n-FET, the CFET structure can be fabricated using a single film. Based on the above-mentioned property, we design the p- and n-FET structure shown in Fig.3 and Fig. 4 and perform the simulation. The double gate structures are used to have better control of the channel. To make the enhanced mode of operation, the HfO2 material was chosen as the gate dielectrics. The device achieves a smaller SS value (~61 mV/dec) (Fig.5 and Fig. 6). Fig. 7 is the majority carrier density plot with different gate biases, the switching between on and off states can be observed. Furthermore, to make the device fabrication process realistic, we proposed a structure that could be built layer by layer (Fig.8). Based on the I-V curve obtained from the 2D simulation result, we built the model and further performed the circuit simulation by LTspice (Fig.9). Set VDD equals to 1.5V, and the middle plot is Vin to Vout of the CMOS inverter. The JTMD materials have a similar transport property as MoS2 and WS2. With the built-in polarization field and a proper design, it is possible to make CFET devices in a single thin film without doping.

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. 

We report our initial results on the fabrication and characterization of 2D materials/III-As semiconductors heterostructures in a planar and helical geometry. These materials promise to support the generation of cyclotron THz radiation with technologically relevant levels of power density (i.e., between 100s mW/cm2 and few W/cm2) under an applied DC bias. An intuitive approach based on a time-of-flight and interference argument shows that radiation frequencies in the THz range are expected from helices with a radius ranging from a few tens to a few hundred nanometers. The exceptional compliance of 2D materials allows them to bend with nanoscale radius curvature without any plastic deformation. A 2D material with high carrier mobility is also required to limit carrier scattering within the helices and thus reduce spectral broadening around the center frequency. h-BN/graphene/h-BN heterostructures will potentially satisfy all the desired attributes to generate cyclotron radiation based on previously reported values of carrier mobility. We create the helical ribbons via guided self-assembly of graphene-based/GaAs/InxGa1-xAs heterostructures with a thickness of ~2-20 nm. This process enables the fabrication of nanoscale-diameter structures whose dimensions can be precisely manipulated in that they depend on residual strain in a nanosheet, its stiffness, and its geometry in the plane perpendicular to its thickness. These are all parameters that can be readily controlled via top-down processing techniques. In our work, multi-layer stacks comprising a GaAs/InxGa1-xAs bilayer and an AlAs sacrificial layer are deposited by molecular beam epitaxy on a (001) GaAs substrate surface. Materials combinations and growth conditions are appropriately selected to establish a large strain gradient across the thickness of the III-As bilayer. We then fabricate h-BN/graphene/h-BN heterostructures on the semiconductor bilayer via polymer-assisted release, transfer of the 2D materials, and vacuum annealing in Ar atmosphere to remove the polymer support. X-ray photoelectron spectroscopy characterizes the removal of the polymer during annealing. Next, the 2D materials/GaAs/InxGa1-xAs nanosheets is patterned into ribbons at a non-zero angle with the softest crystallographic direction in GaAs. Selective etching of the AlAs sacrificial layer results in the nanosheet bending and twisting towards the softest crystal direction (i.e., <100>). We have fabricated structures with a scalable diameter between 30 nm and 800 nm, as estimated by scanning electron microscopy. In addition to illustrating the controlled synthesis of graphene helical ribbons, we present magnetotransport and multi-carrier analysis techniques to characterize mobilities and carrier concentrations in the fabricated heterostructures. A precise knowledge of these parameters will improve our predictive capability of the electromagnetic radiation originated by accelerated charges along the helical path. We fabricate graphene-based/GaAs/InxGa1-xAs Hall bar devices on AlAs-coated substrates and perform variable temperature magnetotransport on a Quantum Design Magnetic Properties Measurement System (MPMS). Multi-carrier analysis techniques are used to shed light on the dominant carrier scattering mechanisms and surface transfer doping of encapsulated graphene on III-As nanosheets. ACKNOWLEDGEMENT. This work was supported by the U.S. AFOSR/Clarkson Aerospace Corporation through award No. FA9550-21-1-0460/UNM 21-1-0460.

Graphene/III-As Nanosheets—Self-Assembly, Electrical Transport and Potential for THz Generation

Two-dimensional transition metal dichalcogenides (2D TMDs) have been extensively studied in recent years due to their remarkable electronic, optical, and mechanical properties. Their ability to withstand high levels of strain without fracture makes 2D TMDs attractive candidate materials for devices such as quantum emitters and wearable energy harvesters. This same ability, however, can have pronounced effects on device performance when unintentional sources of strain cause property changes via deformation potentials and electromechanical coupling. One such source of strain is nanobubbles, which are ubiquitous in mechanically exfoliated 2D samples. When using piezoresponse force microscopy (PFM) to measure the flexoelectric effect in 2D TMDs, we observed that nanobubbles showed greatly enhanced electromechanical coupling compared to flat regions, beyond the difference expected due to the absence of substrate pinning. Measurements of flexoelectric moduli in ostensibly flat monolayers may therefore yield overestimates due to the inclusion of nanobubbles in the analyzed area. Our PFM measurements show consistent reduction in the calculated effective flexoelectric coefficient when the data are filtered to exclude nanobubbles, resulting in a more accurate value for unstrained material. We have also used PFM to characterize the detailed influence of strain, via nanobubbles in exfoliated MoS2 monolayers, on electromechanical behavior in monolayer TMDs, focusing in particular on strain-dependent enhancement of out-of-plane electromechanical responses. Small bubbles with diameters under 100 nm consistently produce enhanced piezoresponse compared to flat regions. Large bubbles with diameters on the order of hundreds of nanometers exhibit an unexpected PFM profile. Rather than increasing monotonically from perimeter to apex, the piezoresponse amplitude of large bubbles reaches its peak near the perimeter and subsequently decreases toward a local minimum at the bubble center. Combined with the calculation of the strain tensor by representing nanobubbles as thin plates and numerically solving the biharmonic von Karman partial differential equation, these results reveal a correlation between electromechanical response and strain derivatives. We posit that this correlation occurs due to their mutual connection to the local symmetry of the crystal. Within the bubble, the crystal’s mirror symmetry is broken, allowing one or more of the out-of-plane piezoelectric tensor elements to become nonzero. The enhanced electromechanical response associated with inhomogeneous strain is likely to have significant implications for a broad range of TMD-based 2D device structures due to the ubiquity of localized strain and the presence of band-edge energy shifts and electrostatic bound charges in those same features.

Effects of Strain and Local Topography on Electromechanical Coupling in Monolayer Transition Metal Dichalcogenides

SU-8 is widely used in a variety of applications for fabricating micro-scale or millimeter-scale structures due to its high viscosity, high optical transmission in the UV range, and excellent mechanical properties. The use of SU-8 for cryogenic applications has been limited because of possible internal stress in SU-8 films due to CTE mismatch with Si, the most commonly used material as a substrate, which can cause adhesion-related problems. We have developed a fabrication process of micro-scale SU-8 structures on a molybdenum (Mo) substrate using polyimide as an interfacial layer. Fabricated SU-8 structures showed good adhesion to the substrate from room temperature to cryogenic temperatures down to 4.2 K. Mo was chosen as a substrate due to its robustness, excellent mechanical strength, and compatibility with laser and CNC machining. SU-8 fabrication was done on 500-micron thick commercially available Mo wafers. The wafers were cleaned using an H2O2/H2SO4 “piranha” solution to remove organic material from the substrate. Atomic force microscopy (AFM) and scanning electron microscopy (SEM) was done before and after cleaning. SU-8 2075 was used to fabricate 250-micron tall structures with different aspect ratios on the Mo substrate. HD-4100 series polyimide was evaluated as an interfacial layer to improve the adhesion of SU-8 to Mo. Thermal shock tests were done using LN2 to test the adhesion of SU-8 with and without the interfacial layer. Shear tests were performed to characterize the adhesion of the SU-8 pillars to the substrate. The Mo wafers were laser-cut using a femtosecond laser to singulate them into pieces with SU-8 structures. These pieces were used as part of a superconducting interconnection scheme for multi-channel DC superconducting flexible cables, wherein the SU-8 structures provided self-alignment and distributed mechanical pressure over the contact area of the flexible cables. This interconnect scheme was demonstrated to be functional over multiple thermal cycles from room temperature to 4.2 K. The results of these experiments provide guidelines and motivation for using SU-8 with a polyimide interfacial layer in cryogenic system applications. Acknowledgment: We gratefully acknowledge funding and technical guidance from Microsoft for this work. We thank the Alabama Micro/Nano Science and Technology Center (AMNSTC) for providing access to fabrication and characterization facilities used in this work.

Fabrication of SU-8 Microstructures on Bulk Molybdenum Substrates for Cryogenic Applications

The need for higher power RF and energy conversion electronics has motivated the search for new device heterojunctions beyond what can be grown using conventional techniques. Instead, we can conceive of new material layer combinations that result in higher performance transport characteristics, e.g., channel conductivity, breakdown voltage, and heat dissipation. However, realizing a high-quality bonded interface has several challenges including the production and processing of low-defect thin material layers and reducing the interface trap density. Here, we have fabricated bonded n--GaN/p+-Si diodes to investigate the dependence of interface quality on surface pretreatments and post-bond annealing. Si-doped GaN films were grown on BN-sapphire templates [1] before being exfoliated using stressed Ni-spalling [2]. The GaN films were bonded top (Ga-polar)-side down onto (100) P-doped Si. IV and CV measurements were performed to characterize the transport across and the charge at the interface. Conducting scanning probe measurements were performed on the GaN surface to characterize the bond areal uniformity. These results are generally applicable to the optimization of interface properties for novel bonded junctions. [1] M. Snure, G. Siegel, D. C. Look, and Q. Paduano, J. Cryst. Growth 464, 168 (2017). [2] E. W. Blanton, M. J. Motala, T. A. Prusnick, A. Hilton, J. L. Brown, A. Bhattacharyya, S. Krishnamoorthy, K. Leedy, N. R. Glavin, and M. Snure, Small 17, 2102668 (2021).

Investigation of Bonded GaN-Si p-n Junction Interface Properties

Defying the isotropic nature of the conventional chemical etch, metal-assisted chemical etching (MacEtch) has allowed spatially defined anisotropic etching by using patterned metal catalyst films to locally enhance the etch rate of various semiconductors [1]. Significant progress has been made on achieving unprecedented aspect ratio nanostructures using this facile approach, mostly in solution. However, the path to manufacturing scalability remains challenging, because of the difficulties in controlling etch morphology including the minimization of porosity and aggregation, and etching uniformity. Taking MacEtch from liquid phase to vapor phase completely will eliminate surface tension, allow independent control of the partial pressure, injection timing and pattern of each etchant, while preventing the movement of the metal-catalyst films. Prior demonstrations of VP-MacEtch utilize thermally generated vapor by suspending the sample over a heated bath of either HF/H2O2 or HF with atmospheric O2 as the oxidant [2-4]. However, the presence of H2O2 in the vaporized solution serves to increase porosity with little impact on the etch rate compared to ambient oxygen [2,4]. The use of O2 as the oxidant limits the range of etching control, as the molar ratio may only be controlled through the dilution of HF. This approach leads to etch rates substantially lower (0.1-0.4 µm/min [1-3]) compared to the liquid phase (>3 µm/min [5]). Although increasing the concentration of HF does improve the etch rate, because of the fixed oxidant supply as the vapor flows across the sample the O2 becomes depleted leading to non-uniform etching and failure in pattern transfer. Here, we demonstrate a programmable vapor-phase MacEtch (VP-MacEtch) approach, with independent control of the etchant flow rates, injection and pulse time, chamber pressure and temperature, as well as UV irradiation. Silicon (Si) nanostructures are demonstrated with each of these parameters systematically varied synchronously or asynchronously, moving MacEtch closer to a manufacturing technique for versatile arrays of 3D Si micro and nanostructures.[6] Figure 1 presents a fully computer-controlled programmable VP-MacEtch system that operates under vacuum with an N2 carrier gas and representative structures produced, with unprecedented features. This work was supported in part by United States Army Research Office Award No. W911NF2110337 , National Science Foundation ECCS #2200651, and a gift from Lam Research. [1] X. Li and P.W. Bohn, “Metal-assisted chemical etching in HF/H2O2 produces porous silicon,” Appl. Phys. Lett., 77, 2572 (2000). [2] Hildreth, O. J., & Schmidt, D. R. (2014). Vapor Phase Metal-Assisted Chemical Etching of Silicon. Advanced Functional Materials, 24(24), 3827–3833. [3] Kim, J. D., Kim, M., Chan, C., Draeger, N., Coleman, J. J., & Li, X. (2019). CMOS-Compatible Catalyst for MacEtch: Titanium Nitride-Assisted Chemical Etching in Vapor phase for High Aspect Ratio Silicon Nanostructures. ACS Applied Materials and Interfaces, 11(30), 27371–27377. [4] Romano, L., Kagias, M., Vila-Comamala, J., Jefimovs, K., Tseng, L. T., Guzenko, V. A., & Stampanoni, M. (2020). Metal assisted chemical etching of silicon in the gas phase: A nanofabrication platform for X-ray optics. Nanoscale Horizons, 5(5), 869–879. [5] Balasundaram, K., Sadhu, J. S., Shin, J. C., Azeredo, B., Chanda, D., Malik, M., Hsu, K., Rogers, J. A., Ferreira, P., Sinha, S., & Li, X. (2012). Porosity control in metal-assisted chemical etching of degenerately doped silicon nanowires. Nanotechnology, 23(30), 305304. [6] Janavicius, L. L, Michaels, J. A, Chan, C., Sievers, D. J, Li, X. (2023). “Programmable Vapor-Phase Metal-Assisted Chemical Etching for Versatile High-Aspect Ratio Silicon Nanomanufacturing,” Apph. Phys. Rev. accepted.

Realization of Vapor-Phase MacEtch: Mechanism, Programmability and Scalability

Wireless interconnected devices have become ubiquitous, with many transformative applications emerging as sensor nodes that scale to smaller dimensions and higher node density. Energy harvesting for sensor systems at the millimeter-scale and microscale has become paramount, where functionality and system lifetime is determined by available power. Energy can be harvested through optical, radio-frequency, mechanical, piezo, thermoelectric and many diverse means [1]. Optical energy harvesting via photovoltaic cells scales efficiently down to the microscale, including sources from outdoor sunlight, indoor lighting, and near-infrared illumination (NIR ~ 850 nm, particularly for biomedical implantable sensors[2]). GaAs/AlAs photovoltaics (PV) provide high power conversion efficiencies for these sources across a broad range of optical spectra Furthermore, GaAs-based PV provides a platform for integrated optoelectronic devices that can be used for low-power optical communications. In this work, we present thin (<8 µm) GaAs PV cells for energy harvesting in microscale systems and heterogeneous integration approaches with low-power CMOS electronics. The PV cell structures consist of a single or dual-junction devices that were grown epitaxially by external foundries. Single junction devices are designed for optical response ranging from outdoor sunlight to 850 nm monochromatic illumination, where lateral series-connected devices may be fabricated to step up voltage output for energy harvesting. Dual junction “segmented” PV devices are designed for monochromatic illumination at 850 nm with target applications for bio-implantable systems. Devices were fabricated using previously established etching, photolithography, and metallization technologies. SiNx passivation layers are used on mesa devices, which also serve as electrical isolation for bonding pads metal interconnects. Fabricated devices are mounted epi-side down on glass substrates for substrate removal using wet chemical etching facilitated by an InGaP etch stop layer. A substrate transfer process is used to flip substrates to a sapphire substrate for device testing or flip chip bonding to silicon CMOS. Single junction and dual-junction PV devices show power density on the order of 1 µW/mm2 under mild 850 nm irradiation with an efficiency >20 %. Experiments using substrate removal utilized a new dual-junction epitaxial growth run where devices exhibited a diode blocking behavior attributed to an improper tunnel junction. Nevertheless, substrate removed devices exhibit power generation and integrity of electrical behavior for both frontside and substrate removed backside illumination. Further progress on substrate removed microscale PV harvesters and flip-chip bonding for device integration will be presented. The authors gratefully acknowledge the National Science Foundation award CBET-2129817 and the National Institute of Health award 1RF1NS128667. J. D. Phillips, Frontiers in Nanotechnology, 3, 633931, 2021 E. Moon et al, … J. D.Phillips, ACS Photonics 8, no. 5 (2021)

Substrate-Removed GaAs Photovoltaic Cells for Microscale Energy Harvesting

2D-layered metal-carbide MXenes have emerged as promising earth-abundant materials for electrocatalysis and energy storage due to their exceptional combination of high conductivity and high surface area. Large scale synthesis of MXenes offers the potential for low-cost device applications, but this goal demands integration with advanced manufacturing approaches such as 3D printing and methods for tuning MXenes’ electrical properties. Here we present two complementary strategies to address these practical limitations of MXenes. The low chemical activity of pristine MXenes such as Ti3C2Tx, and limited active site density inhibit MXenes as practical electrocatalysts for hydrogen evolution reaction (HER). We present a simple and scalable nitrosulfurization method for overcoming these limitations via interfacial doping and structural modification with nonmetallic electron donors (N and S) by heat treatment of 2D titanium carbide (Ti3C2Tx) MXene with thiourea. XPS measurements show substitution of N and S occurs at the basal plane with controllable compositions ranging from 2 - 4 at. % (Sulfur), and 5-15 at. % (Nitrogen) depending on the thermal annealing conditions. HRTEM, SEM, and AFM characterization illustrate simultaneous structural changes from planar nanosheets to hexagonal-nanoplate-decorated nanosheets. XRD reveals increased interlayer spacing after N,S doping, which is expected to increase the diffusivity of electrolytes into the layers and enhance electrocatalytic activity. The optimally N,S doped Ti3C2Tx MXene exhibits a high concentration of Ti-S and Ti-N bonds , yielding a low overpotential of –260 mV and a Tafel slope of 85 mV/dec at a current density of 10 mA/cm2 in 0.5 M H2SO4—3X lower than pristine Ti3C2Tx. This strategy to improve electrocatalytic activity of Ti3C2Tx MXene for hydrogen evolution could open the possibility for manipulating the electrocatalytic performance of a broad range of MXenes. Finally, towards the goal of facilitating device integration of MXenes, we have developed MXene coatings that, when applied on 3D printed conductive lattices, can significantly enhance the specific capacity of microscale porous carbon supercapacitor electrodes. Electrochemical impedance spectroscopy illustrates the capacity for these 3D MXene structures to offer high areal capacitance will delivering low electrode resistance for fast charging and discharge. Mechanical measurements of these electrodes show that integration of 2D MXenes with 3D lattices provides a means for enhancing the electrochemical performance while precisely controlling mass and device geometry.

Anionic Engineering and 3D Integration of 2D Ti3C2Tx MXene for Electrocatalysis and Energy Storage

The urgent need for high-efficiency, low-cost, and environmentally friendly solar cell technology compels new research into innovative solar materials that are stable, earth-abundant, and benign for the development of sustainable thin-film photovoltaics (PVs). Antimony selenide (Sb2Se3) is one such solar-absorbing material that has recently emerged as a promising alternative to CdTe (cadmium telluride) solar cells. CdTe solar cells represent the second-largest PV technology on the market, but contain toxic compounds that have been demonstrated to leach toxins into the soil and water table when left to decompose in landfills. In moderate quantities, the constituent components of Sb2Se3 are inexpensive to source and are non-toxic to humans and the ecosystem [2-3]. Similar to CdTe, Sb2Se3 is a simple binary compound with just one stable phase and stoichiometry – unlike the multivalent copper selenide (CuSe) or tin selenide (SnSe) binary systems. Sb2Se3 exhibits a direct bandgap of 1.1-1.3eV, which approaches the ideal Shockey-Queisser value for single-junction solar cells and demonstrates efficient light harvesting with an absorption coefficient of 105cm-1 in the near-infrared region below about 1000 nm. The >30% theoretical efficiency of Sb2Se3 cells suggests a comparable efficiency to existing CIGS and CdTe solar cells. Other research shows the efficiency of Sb2Se3 thin-film solar cells has improved from 0.66% in 2009 (Nair et al) to 6.6% and 7.6% in 2018 by improving the crystallinity of Sb2Se3 films (Choi et al, Zhou et al). In 2019, the implementation of a one-dimensional (1D) crystal structure improved construction of Sb2Se3 solar cells and resulted in an efficiency of 9.2%. However, these Sb2Se3 solar cells typically use CdS as a n-type partner and therefore are not environmentally friendly due to the toxicity of cadmium. For this reason, we developed and implemented a titanium dioxide (TiO2) n-type partner for the Sb2Se3 solar cells. This paper explores the process of spin-coating fabrication for TiO2 as an n-type partner using three different solutions on FTO-coated soda-lime glass substrates, the deposition of Sb2Se3 for the absorption layer, and nickel deposition by thermal evaporation to construct the complete solar cell. In addition to fabrication processes, we conducted optical-electrical and materials characterization of these TiO2/Sb2Se3 cells to determine their efficiency and investigate their effects on the solar cell performance.

Development of Sustainable Non-Toxic TiO2/Sb2Se3 Solar Cells for Renewable Energy Applications

Semiconductor lasers have a wide range of applications in industry and our daily life. Vertical-Cavity Surface-Emitting Lasers (VCSELs), developed from the 1980’s, have several advantages, compared to edge-emitting lasers, such as wafer-scale testing, uniformity, scalability, circular beam, single-mode, 2D array, etc. A VCSEL consists of a light-emitting active region sandwiched between a top Distributed Bragg Reflector (DBR) and a bottom DBR. In 2017, Apple released the iPhone X embedding VCSELs for face recognition. This was a game-changer. The market is expected to reach $1.9 billion in 2027. Current VCSELs on cell phones for facial recognition are based on 940 nm VCSELs consisting of GaAs/AlAs DBRs grown on GaAs(001) substrates. It is desirable to have longer-wavelength VCSELs, however, because the screen of a smart phone is transparent at longer wavelength (1380 nm) and because of eye safety. The maximum permissible exposure to the retina is higher for wavelength longer than 940 nm. Long-wavelength lasers beyond 1300 nm is commonly fabricated on InP substrates because those wavelengths cannot be accessed by the GaAs/AlGaAs material system. However, it is not practical to grow a DBR on InP because the difference of the index of refraction of InP-based DBR pair, such as InGaAs/InAlAs, is relatively small, compared to that of GaAs/AlAs DBR pair. Thus, many more pairs must be grown to achieve high reflectivity. Also, InP substrates are smaller, more fragile, and more expensive than GaAs substrates. There are several approaches to produce long-wavelength emission from heterostructures grown on GaAs substrates: (1) self-assembled InAs/(In)GaAs quantum dots (QDs), (2) dilute nitride GaInNAs(Sb)/GaAs quantum wells (QWs), (3) wafer bonding of InGaAsP/InP active layers to top and bottom GaAs/AlAs DBRs, and (4) type-II InGaAs/GaAsSb QWs. Each approach has its pros and cons. Here we report on the type-II InGaAs/GaAsSb QWs because QWs have more volume for light amplification than QDs, fewer defects than dilute nitrides, and simpler in processing than wafer bonding. The emission wavelength can be tuned independently by the composition and thickness of the electron and hole quantum wells. There are only a few reports on InGaAs/GaAsSb QWs grown on GaAs substrates. InGaAs and GaAsSb are both compressively strained to GaAs, and tensile-strained GaAsP can be grown to compensate InGaAs and GaAsSb. There is one report of MBE-grown strain-compensated GaAsP/GaAs/GaAsSb VCSELs on GaAs, emitting at 1266 nm. So far, there does not seem to be a report on strain-compensated GaAsP/InGaAs/GaAsSb QWs, let alone VCSELs, on GaAs. In this talk we report on molecular-beam epitaxy (MBE) and characterization of these QWs, specifically investigating the effects of strain compensation. The compositions and layer thicknesses are measured by high-resolution X-ray rocking curves and compared with simulations. Two series of samples were grown. One series have 3 InGaAs/GaAsSb samples grown in the same day: without the GaAsP strain-compensating layer, with GaP and with GaAs0.8P0.2 strain-compensating layers. We found that only the last sample with GaAs0.8P0.2 strain-compensating layers shows a strong low-temperature (LT) photoluminescence (PL) at 1100 nm. The second series also have 3 samples with 2, 4, and 6 nm In0.3Ga0.7As thickness while the corresponding GaAs0.8P0.2 thickness is also adjusted to maintain strain compensation and be within its own critical layer thickness. We found that only the 2 nm-thick In0.3Ga0.7As sample shows a strong LT PL at 1050 nm, indicating 4 nm thickness is already larger than the critical layer thickness. These samples do not have room-temperature (RT) PL, but later samples grown with a higher substrate temperature show RT PL. In conclusion, as expected, strain compensation is beneficial, and we are pursuing longer wavelength emission by adjusting the layer parameters through COMSOL and growth conditions.

The Effects of Strain Compensation in Type-II InGaAs/GaAsSb Quantum Wells Grown on GaAs(001) Substrates

Mid-wave infrared (MWIR) detectors (λcut-off>3μm) are commonly used in medical devices, remote sensing, and spectroscopy [1]. MWIR III-V semiconductors, such as InSb (λcut-off=5.3μm) are more readily fabricated as infrared focal plane arrays (FPA’s) because of their weaker ionic and stronger bonding property compared to II-VIs. III-V-based FPA’s also have the advantage of spatial uniformity, temporal stability, scalability and affordability. This is particularly true in the case of InSb FPAs.[2] To cover the MWIR spectrum and reach the long wave infrared (LWIR) region, type-II superlattices such as InAs/InAsSb, bulk InAsSb on GaSb and metamorphic buffers are used [3]. Metamorphic buffers allow for better coverage of the MWIR spectrum by allowing for increasing antimony percentage in InAsxSb1-x. However, it is challenging to achieve repeatability in the growth of these thick buffer layers (4μm). Previously, direct growth of GaSb on GaAs has been achieved with a threading dislocation density of 108 per cm3 and further reduction is possible with the use of defect filter layers [4]. In this research, we utilize interfacial misfit dislocations to grow fully relaxed InSb on InAs substrate as well as direct growth of AlxIn1-xSb buffer layers on InAs, similar to the GaSb/GaAs system. Developing a fully relaxed, low dislocation density buffer layer will be the basis for developing tunable InAsSb absorbers for MWIR and LWIR applications. The MBE growth of InSb growth on a InAs substrate starts with the removal of native oxide. To grow a fully relaxed InSb layer using interfacial misfit dislocation arrays, the excess arsenic on the InAs surface must be replaced with antimony. We achieve this by eliminating the Arsenic flux. The surface is monitored using reflection high energy electron diffraction (RHEED). The RHEED pattern turns to 4x2 from 2x4 in the absence of arsenic supply which indicates the transition from a group V rich to a group III rich surface. The process is controlled manually by observation of the RHEED pattern transition, and an extra 30 seconds is added after the transition to achieve uniformity over the substrate. The next step involves growth of 500 nm thick Al0.2In0.8Sb and Al0.1In0.9Sb buffer layers to optimize the buffer layers with different growth temperatures. Finally, InSb quantum wells (QWs) are grown for photoluminescence analysis. Both the directly grown AlInSb and InSb epilayers on InAs substrates are analyzed using HR-XRD ω-2θ scans as well as reciprocal space mapping to quantify the dislocation density of the buffer layers. HR-XRD indicates a relaxation of 99.4% for the direct growth of InSb on InAs, and a slightly reduced value for the Al0.1In0.9Sb and Al0.2In0.8Sb epilayers. By using reciprocal space mapping, we are able to determine the screw and mixed dislocation density for the layers. TEM analysis of the samples shows formation of misfit dislocation arrays at the AlInSb/InAs interface. InSb QWs grown with different AlxIn1-xSb barrier layers are investigated by photoluminescence (PL). We will present a detailed analysis of the buffer layers with respect to threading dislocation density using XRD scans as well as TEM images. We will also present a comprehensive analysis of the InSb QWs on the basis of PL and TRPL results. [1] W. L. Sarney, S. P. Svensson, Y. Xu, D. Donetsky, and G. Belenky, “Bulk InAsSb with 0.1 eV bandgap on GaAs,” J. Appl. Phys., vol. 122, no. 2, p. 025705, Jul. 2017. [2] A. Rogalski, “Next decade in infrared detectors,” in Electro-Optical and Infrared Systems: Technology and Applications XIV, Warsaw, Poland, 2017. [3] D. Z. Ting et al., “Advances in III-V semiconductor infrared absorbers and detectors,” Infrared Phys. Technol., vol. 97, pp. 210–216, Mar. 2019. [4] A. Mansoori et al., “Reducing threading dislocation density in GaSb photovoltaic devices on GaAs by using AlSb dislocation filtering layers,” Sol. Energy Mater. Sol. Cells, vol. 185, pp. 21–27, Oct. 2018.

Premium content

Downloads

Next from EMC 2023

Graphene/III-As Nanosheets—Self-Assembly, Electrical Transport and Potential for THz Generation

Similar lecture

Accumulation-Type Ohmic Contacts Between Degenerately Doped and Nearly Intrinsic 2D Semiconductors

Stay up to date with the latest Underline news!

PRESENTATIONS

CONFERENCES

COMPANY

RESOURCES