United States

Abstract Body: The formulation of inks based on 2D materials could enhance the performance of and provide new functional behaviors to printed electronics while retaining scalable manufacturing processes. Recent advances in solution-based exfoliation have demonstrated that the electronic properties of single semiconducting 2D nanosheets can be preserved during ink processing, but there remain several challenges to the production of thin-film transistors based on printed 2D materials. In addition to minimizing inter-sheet resistivity and preserving bulk-like mobilities, the local electronic properties and microstructure of the composite material must be optimized to minimize the resistance of overlapping nanosheets (i.e. junction resistance). To rationally guide the development of 2D inks and related processing, we explored the design principles by integrating device modeling with electrical and scanning probe characterization on transistors consisting of partially overlapping 2D channels (Figure 1a). We examined the limiting factors to the junction resistance by benchmarking a gate-dependent resistor network model with experimentally measured electrical characteristics for model MoS2/MoS2 homojunctions and utilized the model to quantify performance trade-offs determined by nanosheet thickness, percent overlap, sheet resistance and inter-sheet resistivity. Kelvin probe force microscopy (KPFM) was used to measure the surface potential profiles in transistor channels as a function of applied bias conditions and morphological characteristics such as nanosheet thickness. Detailed analysis of the abrupt potential drop measured at the conformal edge provides evidence that the on-state transistor performance of overlapping nanosheets is limited by the local sheet resistance (Figure 1b), which is likely due to weakly screened trapped charges at the edge state. This suggests that passivation and/or functionalization schemes targeting the edges of nanosheets could greatly improve transistor performance. Moreover, we found that screening of the upper portions of overlapping nanosheets produces current crowding at junctions between the edge of one nanosheet and the basal plane of another. Reducing the nanosheet thickness (i.e. the number of layers) increases the carrier concentration of the top nanosheet, thus distributing the current over longer distance and facilitating efficient inter-sheet charge transfer (Figure 2a), which increases the effective mobility and optimum percent overlap (Figure 2b). This provides further motivation to develop exfoliation schemes that preserve intrinsic monolayer properties.

EMC 2021

Towards the Rational Design of Printed 2D Materials

device simulation

kelvin probe force microscopy

printed electronics

2d materials

**[DOWNLOAD THE DRC 2021 DIGEST](https://drive.google.com/file/d/17_-pkYf4IBbVuNYgohTf0iZJORVGp_uN/view?usp=sharing)**

**[DOWNLOAD A COPY OF THE FINAL DRC PROGRAM](https://drive.google.com/file/d/1Ek8UIDCowpLq0z2hXav5tn67FboxS03N/view?usp=sharing)**

For almost eight decades, the Device Research Conference (DRC) has brought together leading scientists, researchers and students to share their latest discoveries in device science, technology and modeling. Notably, many of the first public disclosures of key device technologies were made at the DRC. This year marks the 79th anniversary of the DRC—the longest running device research meeting in the world. As we commemorate this meeting, the high-caliber technical sessions will be highlighted by plenary talks and invited talks by international research pioneers and leaders behind modern electronic technology.

Given the ongoing global health concerns associated with COVID-19 (Coronavirus), the DRC leadership has decided to hold the 2021 Device Research Conference in a virtual (online) format. This follows an enormously successful 2020 DRC held virtually, in which we had record attendance and worldwide participation of more than 875 attendees from 33 countries.

The 2021 Conference will feature:

* Informative, timely short courses in rapidly developing fields
* Oral and poster presentations on electronic/photonic device experiments and simulations
* Plenary and invited presentations given by worldwide leaders
* Evening “rump” session
* Strong student participation and Student Paper Awards

DRC is held in coordination with the Electronic Materials Conference (EMC), which will occur the same week, from June 23-25. As has happened in person in past years, in 2021, the virtual DRC and EMC sessions on the shared day, Wednesday, June 23, will be open to all attendees from both conferences. This recognizes the strong interaction between device and electronic materials research and provides fruitful exchanges of information between attendees of both Conferences. For information on the 63rd Electronic Materials Conference, please visit the [EMC 2021 website.](https://www.mrs.org/63rd-emc/)

2021 DRC individual presentation videos will become available in Underline at the end of each technical session. A recording of each full live session with Q&A will be posted later during the conference. To facilitate re-viewing of recorded talks and sessions, the DRC Underline site will remain open through 11:59pm (US EDT) on July 7th. DRC Conference registration will remain open at www.mrs.org/drc-2021/registration through June 30th.

Thank you for joining us at the 2021 Device Research Conference!

**General Chair**
 Zhihong Chen, Purdue University

**Technical Program Chair**
 Becky (R.L.) Peterson, University of Michigan

**Technical Program Vice-Chair**
 Gregg Jessen, BAE Systems

You can register for the 79th Device Research Conference with the following link. https://www.mrs.org/drc-2021

DRC 2021

For almost eight decades, the Device Research Conference (DRC) has brought together leading scientists, researchers and students to share their latest discoveries in device science, technology and modeling. Notably, many of the first public disclosures of key device technologies were made at the DRC. This year marks the 79th anniversary of the DRC—the longest running device research meeting in the world. As we commemorate this meeting, the high-caliber technical sessions will be highlighted by plenary talks and invited talks by international research pioneers and leaders behind modern electronic technology.

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), 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>

Abstract Body: To alleviate the adverse impacts of utilizing fossil fuel reserves on the environment (global warming, greenhouse emissions), extensive research is being devoted to the development of alternative/renewable energy systems, which include: photovoltaics, fuel cells, batteries, etc. Among them, fuel cells are an excellent solution for energy conversion, where proton exchange membrane (PEM) fuel cells have a wide variety of applications. Some of these applications are portable systems, automotive, etc., where an important reaction occurring at the cathode is the oxygen reduction reaction (ORR). At the current stage in fuel cell technology, platinum (Pt)-based materials are the most practical catalysts1, which, undoubtedly, are the prime choice as the cathode catalyst for the electro-reduction of oxygen, but Pt-based catalysts are expensive. To reduce such costs in commercially viable fuel cells, extensive research is focused on developing alternative catalysts. Silver-based catalysts show a comparatively high thermodynamic stability and excellent catalytic activity over a wide pH range. The TMCs (O, S, Se, and especially Se-based chalcogenides) have attracted significant attention since selenium-based cluster compounds work. Selenium-based metal-rich TMCs catalysts exhibit good electrocatalytic activity, which is mainly attributed to selenium because it improves the electronic structure of the metal by preventing the electrochemical oxidation of metals in most transition metal chalcogenides, as seen for the cases of cobalt selenide and ruthenium selenide. Here, we present a high yield, industrially scalable, and the first-time report on the synthesis of silver selenide from silver foil and selenium powder using a two furnace atmospheric pressure-chemical vapor deposition (AP-CVD) system. We grew low temperature, LT-β-Ag2Se on Ag foil in the AP-CVD system using thermal annealing and leading to a hollow fern-like morphology material and its first-ever reported application as an ORR cathode catalyst. The exfoliated β-Ag2Se is characterized using XRD, EDS, HRTEM, AFM, and HRSEM to determine its stoichiometry and its hollow layered fern-like morphology. Differential scanning calorimetry (DSC) further confirms that the final product is the low-temperature phase β-Ag2Se. Electrochemical oxygen reduction reaction (ORR) of exfoliated β-Ag2Se exhibits sharp oxygen reduction current with an onset potential of 0.88 V/RHE under alkaline conditions, indicating the oxygen reduction property of β-Ag2Se. The large value of limiting current (3 mA cm-2) as well as small Tafel slope (68.5 mV dec-1) corroborates β-Ag2Se as a superior layered transition metal chalcogenide cathode material suitable for such energy-related applications (typically fuel cells and/or metal-air batteries). References (1) Ostroverkh, A.; Johánek, V.; Dubau, M.; Kúš, P.; Khalakhan, I.; Šmíd, B.; Fiala, R.; Václavu, M.; Ostroverkh, Y.; Matolín, V. Optimization of Ionomer-Free Ultra-Low Loading Pt Catalyst for Anode/Cathode of PEMFC via Magnetron Sputtering. Int. J. Hydrogen Energy 2019, 44 (35), 19344–19356. https://doi.org/10.1016/j.ijhydene.2018.12.206.

Facile and Scalable Ambient Pressure Chemical Vapor Deposition-Assisted Synthesis of Layered Silver Selenide (β-Ag2Se) on Ag Foil as a Possible Oxygen Reduction Catalyst in Alkaline Medium

Abstract Body: Photoelectrochemical (PEC) water splitting is a promising technology for using solar energy to convert water molecules into hydrogen gas. Si’s moderate bandgap, high charge mobility and diffusion length, and extensive technology base enable Si-based photoelectrodes to achieve very good PEC performance with the potential for very low cost. However, Si has poor stability in aqueous solutions, limiting long-term stability of Si photoelectrodes for PEC water oxidation or reduction. Metal-insulator-semiconductor (MIS) photoelectrodes have therefore been widely explored for highly efficient and stable PEC water splitting. However, the insulating oxide that protects the semiconductor layer in an MIS photoelectrode typically must be sufficiently thin – a few nm – to enable carrier transport from the semiconductor to the metal catalyst via tunneling, often degrading photoelectrode stability. In this work, we demonstrate a simple, low cost, and highly scalable method to fabricate MIS photoelectrodes with thick SiO2 insulating layers and localized electrical contacts between the Si absorber and metal catalyst structures. The fabricated photoelectrodes show high efficiency and outstanding stability in aqueous solutions, with photoanode onset potential as low as 0.7 V vs. RHE and saturation current density over 30 mA/cm2 under AM1.5G illumination. Both MIS photoanode and photocathode structures are being explored. In a 7 day stability test, constant photocurrent density was maintained with no apparent degradation in performance. These results demonstrate a low-cost, highly scalable approach for fabrication of efficient and very stable photoelectrodes that is suitable for large-scale commercial fabrication and readily adaptable to a variety of catalyst, insulator, and semiconductor materials.

Low-Cost, Scalable Fabrication of Stable, High Performance Si-Based Metal-Insulator-Semiconductor Photoelectrodes for Solar-Driven Water Splitting

Abstract Body: Ever-increasing energy storage demands for vehicle electrification, consumer electronics, and grid energy storage requires further innovations in their performance and safety. To this end, developing new cathode materials has been the major interest in the Li-ion battery community. While cycling, most conventional cathode materials undergo repeated volume changes during Li-ion insertion/extraction (i.e., cycling), which in turn generates stress to the active material particles [1]. As a result of the tensile stress, particles tend to crack and pulverize, leading to a loss of contact and capacity fading. To address the mechanical instability issue from cathode materials, Dr. Lee et al. [2] developed novel spinel-type Li2Co2-xAlxO4 (where x = 0 – 1.0) as a “zero-strain” cathode material; it has less than 0.02% of the volume change during charge/discharge processes. This low volume change was explained by a suppression of rock-salt to spinel phase transition due to the presence of Al cations located in 16c site in [Li2−yAly]16c[Co2−xAlx−yLiy]16dO4. Actually, operando synchrotron XRD analysis demonstrates no phase transition during cycling [2]. The zero-strain Li2Co2-xAlxO4 cathode can overcome the mechanical instability and offer an extended battery life. On the other hand, electrochemical stability of the Li2Co2-xAlxO4 – electrolyte interface is currently unknown. Although the Al-substitution is an effective approach to stabilize the bulk crystal phase, parasitic reactions occurring at cathode – electrolyte interfaces (CEIs) has been a major issue from different types of spinel materials; e.g., transition metal dissolutions from LiMn2O4 or LiNi0.5Mn1.5O4 [3]. Therefore, it is important to understand the CEI properties of the Li2Co2-xAlxO4 and improving the CEI stability further. In this regard, we examined the effect of LiNbO3 coating on the series of Li2Co2-xAlxO4 (x = 0 – 0.6). The LiNbO3 coating layer can offer a facile Li-ion conduction while passivating the CEI layers. The results show that the LiNbO3 coating enhances the cycle life and rate capabilities of the Li2Co2-xAlxO4 cathodes. Electrochemical impedance spectroscopy (EIS) combined with the distribution of relaxation times (DRT) technique has been studied to identify the improvement mechanisms of the LiNbO3. The aging mechanism of the spinel cathode will be demonstrated by various material characterization and electrochemical analysis. This study will be conducted for conventional Li-ion batteries, but the results will be applicable to all-solid-state batteries via future studies. Reference: [1] D.E. Demirocak, B. Bhushan, J. Power Sources, 280 (2015) 256–262. [2] E. Lee, B.J. Kwon, F. Dogan, Y. Ren, J.R. Croy, M.M. Thackeray, ACS Appl. Mater. Interfaces, 2 (2019) 6170-6175. [3] J.-H. Kim, N.P.W. Pieczonka, Y. Li, ChemPhysChem, 15 (2014) 1940-1954.

Surface-Modified Zero-Strain Spinel-Type Li2Co2-xAlxO4 (where x = 0, 0.3, and 0.60) Cathodes for Lithium-Ion Batteries

Abstract Body: Low work function (WF) materials are necessary for energy storage and conversion devices. Scientific literature is full of explorations made in this field with new and emerging technologies applied to different elements with the purpose of creating low work function materials in the bulk and low dimensional regime. Alkali metals and their alloys with tin, cobalt, indium, etc. have been researched very well in batteries and other energy devices. Alkali metals have been shown to effectively aid in reducing the WF of many metals including Pb, Indium, tin, etc. Particular focus has been laid on Sn/Li alloy system where a work function dip up to 1.25 eV has been shown for a stoichiometric ratio of Sn2Li5[1][2]. Of course, this has been demonstrated to occur in the bulk alloys. However, with the purpose of achieving a similar goal in low dimensions (thin films), we are demonstrating for the first time the formation of a thin film of low work function Sn/Li alloy, formed using physical vapour deposition technique (E-Beam and Thermal Evaporation) at Ultra High Vacuum (UHV) conditions. The experiment utilises the high-end NanoESCA facility at the University of Bristol, UK, where the in situ deposition and the characterisation using X – Ray photoemission spectroscopy (XPS), Ultra-Voilet photoemission spectroscopy (UPS), spot profile low energy electron diffraction (Spa-LEED) techniques is carried out.[3]. In the initial experiments, a single crystal Si substrate was heated at a temperature of 800 oC for the removal of contaminants and Sn was deposited using the E beam deposition while Li was deposited using thermal evaporation method on Si substrate. Si surface was found to be terminated with the oxygen atoms. This should be the reason for the further lowering of WF as oxygen has been found to improve the sticking coefficient between the terminating metal species and the substrate surface. In the beginning, the O terminated Si surface was seen to possess a WF of 4.65 eV and a characteristic 2×1 LEED surface pattern which was then lost due to the disordered Sn and Li layers on the surface. However, Sn 3d peak was seen to shift towards the lower binding energy (B.E.) characteristic of the formation of Sn/Li alloy[4]. The WF was seen to lower to 4.15 eV and the surface was seen to become ordered after going through a series of annealing steps i.e., at 200 oC and 300 oC for 1 hour each and then 350 oC for 2 hours. After the 350 oC anneal, the LEED pattern started emerging. However, the Sn 3d peak was shifted to higher B.E. again which demands further analysis in order to find the optimised stoichiometric ratio between S/Li for ultra-low work function demonstration. [1] K. P. Loh, X. N. Xie, S. W. Yang, J. S. Pan, and P. Wu, “A spectroscopic study of the negative electron affinity of cesium oxide-coated diamond (111) and theoretical calculation of the surface density-of-states on oxygenated diamond (111),” Diam. Relat. Mater., vol. 11, no. 7, pp. 1379–1384, Jul. 2002, doi: 10.1016/S0925-9635(02)00014-6. [2] B. B. Alchagirov, R. K. Arkhestov, and F. F. Dyshekova, “Electron work function in alloys with alkali metals,” Tech. Phys., vol. 57, no. 11, pp. 1541–1546, 2012, doi: 10.1134/S1063784212110023. [3] G. Wan, M. Cattelan, and N. A. Fox, “Electronic structure tunability of diamonds by surface functionalization,” J. Phys. Chem. C, 2019, doi: 10.1021/acs.jpcc.8b11232. [4] D.-T. Shieh, J. Yin, K. Yamamoto, M. Wada, S. Tanase, and T. Sakai, “Surface Characterization on Lithium Insertion/Deinsertion Process for Sputter-Deposited AgSn Thin-Film Electrodes by XPS,” J. Electrochem. Soc., vol. 153, no. 1, p. A106, Dec. 2006, doi: 10.1149/1.2133711.

Investigation of Lithiated Tin (Sn/Li Alloy) Thin Film as a Low Work Function Termination on Silicon/Diamond Substrates

Abstract Body: Zinc germanium nitride (ZnGeN2) is the II-IV-N2 analogue of GaN which has a band gap (Eg) very close to that of GaN (~3.4 eV) and a lattice mismatch of <0.1% with GaN [1]. Based on first principles calculations, the predicted valence band offset (VBO) of ZnGeN2 with GaN can be as high as 1.4 eV, [2] which provides great opportunities to design high efficiency InGaN/ZnGeN2 heterostructure quantum wells for visible light emitters [1]. However, there has been no report on the experimentally determined VBO at the ZnGeN2/GaN heterointerface, due to the lack of availability of high quality materials. In this work, we have experimentally determined the VBOs of ZnGeN2 and a 94% ZnGeN2 – 6% GaN alloy ((ZnGe)0.94Ga0.12N2) with GaN using Kraut’s method. The VBO between two materials A and B are determined using the core energy levels (ECL) in bulk A, bulk B and at the A/B heterointerface and the position of the valence band maxima (VBM) in bulk A and bulk B. X-ray photoemission spectroscopy (XPS) was used to measure the ECL and VBM values. To determine the VBO between ZnGeN2 and GaN, a GaN/c-sapphire template, a 16-nm-thick ZnGeN2 film and a 2-nm-thick ZnGeN2 layer grown on GaN template were used as the bulk GaN, bulk ZnGeN2 and ZnGeN2/GaN heterostructure, respectively. ZnGeN2 films were grown on GaN/c-sapphire templates via metalorganic chemical vapor deposition (MOCVD) [3,4]. By using the measured Zn 3d (Ge 3d) core levels from ZnGeN2 and the Ga 3d core levels from GaN, the VBO of ZnGeN2 with GaN was extracted to be 1.45±0.15 eV (1.65±0.15 eV). These values are comparable to the values predicted from first-principles calculations using explicit interface calculations [2]. Similarly, the VBO of (ZnGe)0.94Ga0.12N2 with GaN was determined. The samples used include a GaN/c-sapphire template as bulk GaN, a 20-nm-thick (ZnGe)0.94Ga0.12N2 films as bulk (ZnGe)0.94Ga0.12N2 and a 3-nm-thick (ZnGe)0.94Ga0.12N2 film as the (ZnGe)0.94Ga0.12N2/GaN heterostructure. These samples were grown on GaN/c-sapphire templates via MOCVD. The experimentally extracted VBO of (ZnGe)0.94Ga0.12N2 with GaN was 1.29±0.15 eV. Assuming a linear dependence of the VBO with composition x of (ZnGe)1-xGa2xN2, the predicted VBO of (ZnGe)0.94Ga0.12N2 from the theoretically calculated VBO of ZnGeN2 would be 1.32 eV. Thus, the experimentally measured VBO results agree well with the theoretically predicted values. The conduction band offsets were derived using the determined VBO values and the energy band gap Eg of the materials. The band gaps of ZnGeN2 and (ZnGe)0.94Ga0.12N2 were estimated from the inelastic energy loss features of N 1s peaks in the XPS spectra of 16-nm-thick ZnGeN2 and 20-nm-thick (ZnGe)0.94Ga0.12N2 samples. The Eg values determined by this method were 3.0±0.2 eV for ZnGeN2 and 3.1±0.2 eV for (ZnGe)0.94Ga0.12N2. The lower values of Eg as compared to the predicted band gap values (~3.4 eV) can be due to the presence of disorder in the cation sublattice. In conclusion, the valence band offsets of MOCVD-grown (ZnGe)1-xGa2xN2 with GaN, with x = 0 and 0.06 were determined experimentally using XPS. The measured VBO values are comparable to the predicted values from first-principles calculations. The results from this study will expand device designs based on pure III-nitrides to III-nitrides/II-IV-N2, which can potentially address key challenges in III-nitride based electronic and optoelectronic device technologies. This work is supported by the U.S. DOE (DOE SSL: DE-EE0008718) and by the NSF (DMREF: SusCHeM: 1533957). References 1. L. Han, K. Kash, and H. Zhao, J. Appl. Phys., 120, 103102 (2016). 2. A. P. Jaroenjittichai, S. Lyu, and W. R. L. Lambrecht, Phys. Rev. B., 96, 079907(E) (2017). 3. M. R. Karim, B. H. D. Jayatunga, M. Zhu, R. A Lalk, O. Licata, B. Mazumder, J. Hwang, K. Kash, H. Zhao, AIP Adv. 10, 065302 (2020). 4. B. H. D. Jayatunga, M. R. Karim, R. A. Lalk, O. Ohanaka, W. R. L. Lambrecht, H. Zhao, and K. Kash, Cryst. Growth Des., 20, 189 (2020).

Experimental Determination of Valence Band Offsets of ZnGeN2 and (ZnGe)0.94Ga0.12N2 with GaN

Abstract Body: ZnGeN2 and GaN are nearly lattice matched and each have band gaps of approximately 3.4 eV. The large band offset of 1.4 eV in the conduction band results in a type II band alignment that has great potential for novel device structures such as high-performance LED structures that emit wavelengths beyond green [1,2]. Recently published work included theoretical predictions revealed a slightly positive mixing energy, indicating a tendency toward phase separation [3], and the lowest energy configuration to be the octet-rule-preserving Pmn21 phase for ZnGeGa2N4. Other compositions can be rendered by random stacking of ZnGeN2 and GaN layers along the orthorhombic b axis in octet-rule-preserving (and hence lower energy) phases. [3] MOCVD growth of this alloy on c-, r-, and a-plane sapphire and c-GaN/sapphire substrates showed that films of 50-50 composition exhibit better surface morphologies when grown on r-sapphire substrates. A surprising trend of increasing Zn incorporation with increasing Ga was noted. The optimal growth temperature and pressure were determined to be 670 0C and 550 torr at which the highest growth rate, 3.46 µm/hr, was obtained for a film grown on r-sapphire. This film also yielded a wurtzite (110) 2θ-ω XRD diffraction peak at 2Θ = 57.700 with FWHM of 0.760 and the lowest RMS surface roughness over an area of 1 μm2 , ~ 10 nm measured by AFM. [4] The only other experimental work on this alloy reported to date employed a gas reduction nitridation method for synthesis of powders of different compositions, from pure ZnGeN2 to a 50-50 mixture, for photocatalytic applications [5]. Recent progress in growth and characterization is reported here. Atomic-resolution HAADF-STEM images show single-crystal atomic arrangements within 2-3 nm of the substrate interface. The lattice parameters a, b and c measured from these images are 6.429 ± 0.012 Å, 5.585 ± 0.079 Å, and 5.252 ± 0.085 Å, respectively. Introduction of a low-temperature ZnGeN2 buffer layer (480 oC at 600 torr) improved the surface morphology, resulted in higher Hall mobilities, and gave band edge photoluminescence at approximately 3.5 eV, close to the predicted value for the Pmn21 phase. [3] Evaluation of several growth experiments with respect to resulting surface morphology and x-ray rocking curve peak line widths show that the optimal growth conditions for ZnGeGa2N4 with low-temperature ZnGeN2 buffer layers differ significantly from the optimal growth conditions for ZnGeN2 without the low-temperature ZnGeN2 buffer layers. To obtain optimal, nearly stoichiometric ZnGeGa2N4 films, the precursor DEZn flow rate was reduced by nearly half of that used in the same system for optimal ZnGeN2 growth at the same temperature. This reduction in DEZn flow rate also allows for the achievement of higher growth temperatures for ZnGeGa2N4 than for ZnGeN2 while avoiding Zn depletion. Growth of a quaternary alloy with composition approximately 25:75% ZnGeN2 : GaN also resulted in a continuous film with similar surface morphology, and an rms surface roughness of 10.2 nm over an area of 1 μm2. This work is supported by the U.S. DOE (DOE SSL: DE-EE0008718) and by the NSF (DMREF: SusCHeM: 1533957). [1] L. Han, K. Kash, H. Zhao, J Appl Phys 120, 103102 (2016) [2] M. R. Karim, H. Zhao, J Appl Phys 124, 034303 (2018) [3] B.H.D. Jayatunga, S. Lyu, S. Kumar, K. Kash, W. R. L. Lambrecht, Phys Rev Mat 2 (2018) [4] B. H. D. Jayatunga, Md R. Karim, R. A. Lalk, O. Ohanaka, W. R. L. Lambrecht, H. Zhao, and K. Kash, Crystal Growth & Design 20, 189-196 (2020) [5] T. Suehiro, M. Tansho, T. Shimizu, J Phys Chem C 121, 27590 (2017)

Progress in MOCVD Growth and Characterization of ZnGeGa2N4 Films

Abstract Body: There is a significant scientific and technological interest in the epitaxial integration of ferromagnetic or antiferromagnetic materials with the topological insulators (TI). This allows the introduction of the ferromagnetic order into a topological insulator system and may lead to the development of novel spin electronic devices. It is anticipated that these heterostructures can be used as novel magnetoresistive random access memory (MRAM) devices with high charge-to-spin conversion efficiency. This implies that TI-based heterostructures can switch between 0 and 1 memory states much more efficiently, while consuming lower energy than the state-of-the-art magnetic tunneling junction-based heterostructures that use transition metals. The TI-based devices will be less susceptive to weak disorder and perturbations since writing process will occur via conventional writing field while electrical read out process will be topologically protected. A key requirement for an operational heterojunction is a successful coupling of a TI with the magnetic material, which is facilitated by “atomically-clean” and abrupt junction interface. This should involve low-temperature deposition of the magnetic layer on the TI surface. This eliminates usage of the standard magnetic materials growth techniques, such as molecular beam epitaxy (MBE) and pulsed laser deposition, as they require the substrate temperatures greater than 300-350 0C, above what TIs can survive. Here, we report on the innovative approach to grow a room-temperature antiferromagnetic semiconductor (MnTe) using atomic layer deposition (ALD) and to epitaxially integrate it with the topological insulator (Bi2Te3). MnTe films were deposited at <100> GaAs and <111> InP. While the MnTe at <100> GaAs were polycrystalline, epitaxial growth was achieved at closely lattice-matched <111> InP at temperatures as low as 120 0C. Bi2Te3 was grown by MBE at c-Al2O3, ex-situ transferred into the ALD system, and used as a template for MnTe growth. High-resolution X-ray diffraction studies demonstrated that epitaxial MnTe growth was achieved at 120 0C. Transmission electron microscopy showed that the MnTe / Bi2Te3 interface was atomically sharp. No amorphous and / or disordered regions were present at the interface within the imaged regions. Magnetotransport properties of the ALD-grown MnTe were also studied and will be reported here. In summary, ALD was successfully used for the low-temperature epitaxial integration of MnTe antiferromagnetic semiconductor with the Bi2Te3 topological insulator. This opens the path for the realization of near-room temperature energy-efficient spintronic devices.

Low-Temperature Epitaxial Growth of Anti-Ferromagnetic MnTe at Bi2Te3

Abstract Body: Dimensionality is the determining critical parameter in any material. Graphene and transition metal chalcogenides are two-dimensional (2D) layered nanomaterials which demonstrate wide array of physical and chemical properties when approaching few-layer thicknesses [1-2]. Large lateral size of these van der Waals nanomaterials with thinner mono- or few-layered flakes possess higher aspect ratios, which makes them suitable for electronic and optoelectronic applications. Among the most reliable techniques for exfoliation, sonication-assisted liquid-phase exfoliation (LPE) is considered to be a simple and cost-effective method for preparing graphene and its 2D inorganic counterparts at reasonable sizes and acceptable levels of defects. Although there were rapid advances in this field, improper sonication may result in unstable dispersions with wide flake sizes and thicknesses distributions, impurities and defects. Previous studies were mainly focused on the effects of solvent selection (predominantly, using high-boiling point solvents or surfactants), sonication time, and power input (usually, high power from probe/tip sonication can cause significant damage to the material). However, the effect of the sonication frequency is poorly understood and often ignored resulting in a low exfoliation efficiency. Here, we demonstrate that simple mild bath sonication at high frequency at relatively low powers contributes to the thickness, size and quality of the final exfoliated products. We show that monolayer graphene flakes can be directly exfoliated from graphite using only ethanol as a solvent at a reasonable sonication time by increasing the frequency of the bath sonicator from 37 kHz (which is usually used) to 80 kHz. The key mechanism involved is the generation of small-sized bubbles resulting from higher frequencies, which can easily penetrate between the interlayer spacing of the 2D materials to facilitate the delamination process with reduced damage to the material [3]. Detailed morphology studies by atomic force microscopy (AFM) indicate that the obtained product is dominated by large lateral size (10-15 μm) monolayer graphene flakes. High resolution TEM (HRTEM) show that the graphene flakes are of high-quality without any significant structural defects, although X-ray photoelectron spectroscopy (XPS) shows evidence of a small oxide population. Additionally, we show that this facile technique can be applied to other inorganic 2D nanomaterials such as digenite (Cu9S5) and silver sulfide (Ag2S). This simple and effective method facilitates graphene and transition metal chalcogenides’ processing for a wide range of applications. References [1] Coleman et.al, Science, 2011, 331, 568-571. [2] Novoselov et.al, PNAS, 2005, 102, 10451-10453. [3] Merouani et.al, Ultrason Sonochem., 2013, 20, 815-819.

Higher Ultrasonic Frequency Liquid Phase Exfoliation as a More Efficient Method to Deposit Monolayer to Few-Layer Flakes of 2D Layered Materials

Abstract Body: Two-dimensional transition metal carbides and nitrides, so-called MXenes, have quickly attracted intensive attention and have found quite promising applications in various fields, such as water desalination, energy storage, catalysis, etc. These cutting-edge applications require the production of high quality MXene nanosheets with a high concentration. However, this has proven to be quite challenging. Here in this talk, I will describe the synthesis of high-quality MXene nanosheets, followed by the oxidation stability mechanism of MXene aqueous solutions, which is quite important for the long shelf life and is the prerequisite for the industrial application of MXenes.1 Then I will show the importance of the viscous inks in the efficient fabrication of high-performance transparent conductive films/coatings,2 scalable production of micro-supercapacitors assisted by the additive-manufacturing techniques (Figure 1).3 The ink viscous nature also allows the MXene nanosheets to perform as a conductive binder for Si nanoparticles, resulting in high mass-loading MXene/Si anodes with an ultrahigh areal capacity (Figure 2), which is 5 times higher than that of commercial anode.4 In addition, I will show the formulation of organic MXene inks for scalable additive-free printing of energy storage devices, as well as the formulation of composite ink for Lithium-sulfur batteries (Figure 3).5 We therefore believe the high-quality MXene inks hold a bright future for the next-generation energy storage devices at a low cost.

High-Quality MXene Inks for Energy Storage

Abstract Body: Sustainable energy storage devices demand new materials for energy storage systems, which alleviate their cost and increase longevity. A prominent energy storage technology for modern applications is Lithium-ion batteries. In this regard, two-dimensional (2D) materials attracted substantial and considerable attention due to their unique properties and abundant potential in various applications, including batteries1. Controllable synthesis of 2D materials with high quality and better efficiency is essential for their large scale applications, such as their functions as electrode material in batteries. The methods for the synthesis of two-dimensional materials include exfoliation, solvothermal, and chemical vapor deposition (CVD) routes, among which CVD offers better quality, efficiency, and consistency. In this perspective, the family of 2D transition metal di-chalcogenides (TMDCs) gained significant attention for their ability to store metal ions such as Li, Na, and Mg. TMDCs of group 6 transition metals (MX2 where M = Mo, W, and X = S, Se, Te) have a lamellar structure (space group P63/mmc) similar to graphite but with larger interlayer spacing. Tungsten di-chalcogenides are significant here because of the larger size of W that provides a further alteration of the 2D structure and has been successfully utilized for various applications such as photodetectors, field-effect transistors (FETs), etc. The typical group 6 TMDC lattice structure show W atoms confined in a trigonal prismatic coordination sphere neighbored to Se atoms. Because of its very high density (~9.32 g cm−3), WSe2 also has a high volumetric capacity, thereby proving it as a prospective LiB electrode material2. Our work focuses on a facile synthesis of 2H-WSe2 on W foil in the ambient-pressure chemical vapor deposition system using only Argon as carrier gas during the reaction. Extensive characterization of the bulk and exfoliated material confirm that the as-synthesized 2H-WSe2 is layered (i.e., 2D). XRD (X-Ray Diffraction) confirms the phase. At the same time, HRSEM (High-Resolution Scanning Electron Microscopy), HRTEM (High-Resolution Scanning Electron Microscopy), and AFM (Atomic Force Microscopy) clarify the morphology of the material. FIB-SEM (Focused-Ion Beam Scanning Electron Microscopy) estimates the depth of the 2H-WSe2 formation on W foil around 5-8 μm and Raman/UV-Vis measurements prove the quality of the exfoliated 2H-WSe2. The redox processes of Lithium-ion Battery (LiB) studies show an increase in capacity until 500 cycles. On prolonged cycling, the discharge capacity till the 50th cycle at 250 mA/g, the material shows a stable capacity of 550 mAh/g. These observations indicate exfoliated 2H-WSe2 has promising applications as LiB electrode material. References (1) Xia, H.; Xu, Q.; Zhang, J. Recent Progress on Two-Dimensional Nanoflake Ensembles for Energy Storage Applications. Nano-Micro Lett. 2018, 10 (4), 1–30. https://doi.org/10.1007/s40820-018-0219-z. (2) Share, K.; Lewis, J.; Oakes, L.; Carter, R. E.; Cohn, A. P.; Pint, C. L. Tungsten Diselenide (WSe2) as a High Capacity, Low Overpotential Conversion Electrode for Sodium-Ion Batteries. RSC Adv. 2015, 5 (123), 101262–101267. https://doi.org/10.1039/C5RA19717A.

Scalable Synthesis of Few-Layered 2D Tungsten Diselenide (2H-WSe2) Nanosheets Directly Grown on Tungsten (W) Foil Using Ambient-Pressure Chemical Vapor Deposition for Reversible Li-Ion Storage

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