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Exchange bias, a magnetic phenomenon emerging at the interface between a ferromagnet (FM) and an antiferromagnet (AFM), originates from the pinning of spins in the FM layer by the adjacent AFM layer, effectively stabilizing the FM against the environmental stray magnetic fields. This phenomenon has been implemented in a wide range of technological applications including magnetic memories, magnetic read heads, and sensors, and plays the foundational role for advanced spintronics. Here, we report an approach to establishing strong exchange bias in the 2D magnet/oxide heterostructure by a single-step process — atomic layer deposition (ALD). The exchange bias we created is controllable in the range of ~300 to 1500 Oe by replacing different oxides in the heterostructure. Hence, this systematic work elucidates the essential role of ALD-enabled oxidization of layered magnets in the formation of exchange bias and establishes ALD of oxides as a facile, controllable, and generally effective approach to creating giant exchange bias in vaW magnets, representing an integral advance towards practical vdW spintronic devices.

EMC 2022

Facile Integration of Giant Exchange Bias in 2D Magnet/Oxide Heterostructures

2d magnet

heterostructure

exchange bias

After two years of virtual conferences, we're excited to host EMC 2022 in person at The Ohio State University in Columbus, Ohio. In addition to cutting-edge technical presentations given in multiple parallel sessions, opportunities to network with colleagues will be present throughout the conference. The size and format of the meeting makes networking easy, whether you have been coming to the conference for many years or are a first-time attendee.

EMC is coordinated with the Device Research Conference (DRC), which will be held the same week, from June 26-29. This recognizes the strong interaction between device and electronic materials research and provides fruitful exchange of information between attendees of both Conferences.

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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.

technical paper

Layered chalcogenides are promising materials for future (opto-)electronic applications. ' 2 The semiconductor tin selenide (SnSe) is a member of the monochalcogenide (MX) family, which feature functionality including domain-switching behavior, ferroelasticity, thermo-, piezo- and ferroelectricity.” ~ Orthorhombic a-SnSe has strong in-plane anisotropy with implications for thermal, electronic, and optical properties. It has been studied for next-generation microelectronics, photonics and energy-conversion technologies, and has been the focus of a theoretical proposal for ultra-fast, non-thermal optical domain switching. ’~ Control of rotational domains (i.e., twins) during SnSe thin-film synthesis is key to enable high-quality, single-crystalline SnSe for the proposed applications. This work focusses on MBE of SnSe. We demonstrate (1) a fast and easy method to probe rotational domains in SnSe thin films and (2) a solution to overcome the formation of rotational domains by focusing on symmetry and lattice-matched vdW epitaxy of SnSe on a-plane sapphire surfaces. When orthorhombic SnSe (in-plane lattice parameters; a = 4.15A and b = 4.44A) is epitaxially grown on cubic MgO (a = 4.21A), various rotational domains are formed as a result of the various symmetry structure of both materials. ~ The 2-fold rotational symmetry of SnSe combined with the 4-fold symmetry of MgO results in the formation 90° SnSe twins, and a high density of grain boundaries upon closure of the epitaxial film. Characterizing rotational domains in ultra-thin films of 2D materials is generally challenging (in-plane HR-XRD, ‘large-area’ cs-TEM imaging, etc.). We show that, thanks to the optical anisotropy of a-SnSe in the visible (An = 0.88) | 5 supported by an optical model based on the reflectivity of linearly-polarized light, 90° SnSe twins are easily distinguishable using polarized optical microscopy. When studied under cross-polarization at 45° with respect to the SnSe optical axis, slightly increasing or decreasing the angle of the polarizer with respect to the analyzer enables the color splitting of 0°-oriented and 90°- oriented domains into blue and yellow, respectively, when illuminated with white light. We first demonstrate this method on thicker SnSe epitaxial crystallites (~5Onm), using polarized Raman spectroscopy for validation, and we then apply it to thinner (~5nm) epitaxial SnSe films. The distribution of blue and yellow pixels in the optical image enables the quantification of rotational domains and confirms the presence of a high density of 90° twins on MgO. To overcome the formation of 90° twins, we grow epitaxially on a-plane sapphire [a-AI,0..(1 1-20)] substrates. Similarly as a-SnSe, the surface unit of OAI,0.3(1 1-20) can be constructed using dissimilar in-plane lattice parameters; a = 8.24A andb=12.99A. This favors single-oriented domain epitaxy of (2 x 3) units of SnSe on a-Al., O,,(11-20), explained by the symmetry match and small lattice mismatch in both in-plane directions, and confirmed 3 experimentally by our polarized reflectivity method. The developed optical method and epitaxy on a-plane sapphire represent a very useful combination of film metrology and growth methodology to realize high-quality, single-crystalline epitaxial SnSe thin films free of rotational twin domains. We will also highlight our epitaxial growth techniques, especially a comparison between solid-source and plasma-assisted methods. Singh A et al ACS Photonics 2020, 7 (12) Liu Y et al Nat. Rev. Mater. 2016, 1 (9) Zhou J et al Nano Lett. 2018, 18 (12) Gomes C et al J. Appl. Phys. 2020, 128 (12). Chang K et al Nano Lett. 2020, 20 (9) Chen G et al Prog. Mater. Sci. 2018, 97 Zhao D et al Nature 2014, 508 (7496) Jo S et al Adv. Photonics Res. 2021, 2100176. 9) Mortelmans W et al Appl. Mater. Today 2021, 22 10) Nguyen Q et al J. Alloys Compd. 2020, 840

Fast and Easy Optical Imaging and Epitaxial Growth Control of Rotational Domains in SnSe Thin Films

Freestanding graphene nano- and microstructures have been shown to exhibit controllable electron emission when carrying a current and immersed in an external accelerating electric field. Through the mechanism of Phonon-Assisted Electron Emission, these structures demonstrate electron emission at electric field intensities and lattice temperatures below what would be expected for carbon to demonstrate field emission or thermionic emission, respectively. Emission currents have been measured primarily out of the plane of the device surface, allowing some directional control before the accelerating field is even considered. Thus far, such demonstrations have tended to involve structural dimensions on the order of only a handful of um, and have commonly been fabricated from CVD transferred graphene, flakes, or carbon nanotubes in various vertical and horizontal arrangements. Applied fields for such devices typically approach hundreds of kV/cm, and emission currents rarely leave the nA range. Herein are presented graphene structures with dimensions up to cm, in fields not exceeding 1 kV/cm, and producing emission currents of nearly 10 UA. Quasi-freestanding epitaxial graphene, synthesized from a silicon carbide substrate, offers several advantages compared to transferred graphene or unzipped nanotubes, including greater structural integrity, lower defect density, ease of handling, and ready compatibility with conventional simple photolithographic fabrication techniques. The devices presented here were fabricated with a low-cost, wafer scalable, single-photomask process that does not require material transfer to a secondary substrate and is easily tailored to create variations in design parameters, which allowed multiple batches of devices to be rapidly manufactured with precise variations for the purpose of performance testing. The devices exhibit recognizable patterns of emission current performance relative to device and substrate temperature, including an identifiable turn-on point and emission current maintenance. Device behavior relative to substrate heating identifies the electron-phonon interactions that enable function and current emission, both when device temperature is supplied internally and externally. Emission currents are also observed to follow a performance pattern derived from purposeful device morphology, even exhibiting emission currents in accelerating fields as low as 50 V/cm. Graphene electron emission devices present an opportunity for electron emission in a planar 2D heterostructure environment, beyond even the dimensional capabilities of field emission devices, and below the high operating temperatures of thermionic sources. Through refinements in the design and packaging, such devices, which are arbitrarily scalable between the micron and wafer level, could provide the electron sources for novel applications in Xray generation or electron microscopy.

Electron Emission Sources from Quasi-Freestanding Epitaxial Graphene Planar Devices

High-brightness photoemitters can be employed as electron sources in ultrafast electron diffraction and X-ray free-electron lasers, energy recovery linacs, electron microscopes, electron beam lithography, space propulsion and high-power microwave devices. To yield high quantum efficiencies, high brightness beams require rapid response times and low mean transverse energies (MTE). Recently, negative electron affinity (NEA) photocathodes, consisting of a GaAs wafer and a Cs/O surface layer, have been reported to exhibit both reasonably low MTE and good external quantum efficiencies (EQE) of ~10 ~-10 “. However, NEA cathodes are rarely used due to their significantly complex fabrication process which includes high temperature processing steps, entirely in-situ activation as well as ultra-high vacuum storage and operating pressures. Their stability is not also up to the mark. In this investigation, we have fabricated a Hot Electron Laser Assisted Cathode (HELAC) using electronically tunable negative electron affinity silicon surface. Briefly, the device consists of a three-layer stack of (i) a semiconductor, which absorbs incident photons, (ii) a monolayer of graphene, which acts as the gate, and (iii) an insulator, which allows a voltage drop between the semiconductor and graphene. In this device, an electric field is generated by applying a bias voltage between the semiconductor and graphene which mimics the surface dipole field in an NEA photocathode. Electrons injected into the graphene do not require transport to the emitting surface due to the monolayer thickness of the graphene. This device is air stable with a simple ex-situ fabrication flow while preserving the advantages of NEA photocathodes. We have demonstrated an initial proof-of-concept HELAC device with a psilicon substrate, silicon oxide insulator and monolayer graphene stack and evaluated its performance using a 405 nm CW laser at ~40 mW of incident power. Despite having a non-optimized structure, this device has exhibited a current of ~70 yA (~1.1 mA/cm?), resulting in an EQE of ~0.5%. Semiconductor modeling indicated that EQEs of ~10% and response times in the 1-10 ps range are plausible for this device. Additionally, it is expected that low-MTE is achievable by optimizing the quality of the insulator, the barrier height, and the tunneling mechanism. This is analogous to Cs-based NEA devices, where low MTEs are attainable despite a large electric field which is developed due to the surface dipole.

Hot Electron Laser Assisted Cathode using Electronically Tunable Negative Electron Affinity Silicon Surface

Here, we demonstrate chemical potential control as an effective tool to suppress compensation in Mgdoped nitrogen-polar (N-polar) gallium nitride (GaN) films grown by metalorganic chemical vapor deposition (MOCVD). An increase in nitrogen chemical potential obtained by increasing the process supersaturation is shown to systematically reduce the incorporation of compensating oxygen and nitrogen-vacancy point defects. This is confirmed by photoluminescence and temperature-dependent Hall effect measurements. The suppressed compensation led to an order of magnitude improvement in p-type conductivity with the room-temperature hole concentration, mobility, and resistivity measuring 6x10" cm ™~, 9 cm*/Vs, and 1.1 ohm-cm, respectively. These results are paramount in the pathway towards N-polar GaN power and optoelectronic devices. GaN with N-polar orientation has attracted growing interest toward the development of high-performance electronic and optoelectronic devices such as high-frequency high electron mobility transistors (HEMTs), solar cells, longwavelength LEDs, and ultraviolet photocathodes. A reversal of polarization field direction in N-polar GaN from its metal-polar counterpart allows for device designs that lead to improved performance, for example, enhanced carrier extraction efficiency in InGaN solar cells, enhanced hole injection, suppressed electron overflow and decreased droop in LEDs, improved confinement in the two-dimensional electron gas channel in AlGaN/GaN HEMTs, and improved transistor performance in polarization-engineered tunnel field-effect transistors (T-FETs). These novel device applications based on N-polar GaN can be further improved and optimized with the realization of low-resistivity p-type material. For example, achieving a steep device turn-on in T-FETs necessitates low resistance p-GaN layers, whereas high hole and electron concentrations are required near the p-n junction for optimal band alignment in these devices. Achieving efficient p-type doping in GaN is understood to be challenging due to an interplay between large Mg acceptor ionization energy (150-220 meV), incorporation of compensating point defects and point defect complexes during epitaxial growth, and low mobility values of holes as compared to electrons. Moreover, N-polar GaN offers added material challenges that need to be addressed to achieve high p-type conductivity. For instance, if not controlled, N-polar GaN grows with a rough surface morphology characterized by hexagonal hillocks, and high unintentional defect incorporation, notably oxygen, which incorporates at concentrations >10 ~ cm™~. Oxygen on the nitrogen site (O7) acts as a shallow donor in N-polar GaN with an activation energy of ~29 meV which leads to significant difficulties in achieving p-type conductivity. In addition, the incorporation of nitrogen-vacancy (V)))-related compensating defects is favored in p-type GaN due to low formation energy. While much work has focused on pdoping of Ga-polar GaN, to date, comprehensive electrical characterization and compensation control in p-type Npolar GaN is lacking in the literature. The chemical potential control (CPC) is a predictive approach wherein the dependence of the defect formation energy is theoretically estimated as a function of MOCVD growth parameters. These growth parameters are, for example, the V/IIl ratio, diluent gas, temperature, pressure, and input partial pressures of gas species. Instead of these individual MOCVD “knobs”, supersaturation is employed as a representative thermodynamic parameter. Following the CPC framework, increasing the supersaturation can be shown to increase the formation energy of both compensating defects, On and Vn: In this work, we demonstrate the utility of the CPC scheme in reducing the compensation in ptype N-polar GaN to realize state-of-the-art hole concentration and resistivity.

Chemical Potential Control in p-Type N-Polar GaN

The heterogeneous integration of IIl-nitride materials with other semiconductor systems for electronic devices is attractive because it combines the excellent electrical properties of the Ill-nitrides with other device platforms. Pursuing integration through metalorganic chemical vapor deposition (MOCVD) is desirable because of the scalability of the technique, but the high temperatures required for the MOCVD growth of Ill-nitrides (>1000 °C) are incompatible with heteroepitaxy on some semiconductor systems and fabricated wafers. Thus it is critical to develop IIl-nitride films with good electrical properties at growth temperatures compatible with temperature sensitive substrates. High crystal quality GaN films with reduced impurity levels have been achieved at temperatures as low as 500 °C using pulsed growth methods such as atomic layer epitaxy and flow modulation epitaxy (FME). However, the electrical behavior of doped LT Ill-nitride films is relatively unexplored. In this work, thin Si-doped LT GaN films were grown at 550 °C by atmospheric pressure MOCVD using an FME scheme. Triethylgallium and ammonia were used as the GaN precursors and disilane as the Si dopant. Because of the very low growth rate (0.006 A/s), 1200 FME cycles resulted in approximately 16 nm-thick films. Two different FME Si-doping schemes were investigated. The first series varied the fraction of cycles in which disilane was injected into the growing film. Samples were grown with disilane injected every 20, 10, 5, 3, 2, and 1 cycle. The second series varied the disilane flow while using the standard frequency of disilane injection (1 in 5 cycles). Samples were characterized by Hall measurements and secondary ion mass spectrometry (SIMS). For the disilane injection series films, electron concentrations up to 6.97 x 4018 om”? were achieved, with electron mobilities from 34 to 119 cm vi sl The peak electron concentration was achieved for the sample with disilane injected in 1/3 of FME cycles during growth. The charge dropped off for samples with higher frequencies of disilane injection, likely because of degraded morphology. The Si concentrations measured by SIMS were somewhat higher than the electron concentrations measured by Hall. The background atmospheric impurity concentrations averaged 2.1 xX 1017 em’? for oxygen and 3.9 x 10 0 cm ~ for carbon, with no apparent dependence on Si concentration. The disilane flow series resulted in films with electron concentrations from 5.98 x 10 ~ cm ~ to 5.91 x 10'9 om”? and electron mobilities from 52 to 115 cm? vi s |, with the highest charge achieved with the highest disilane flow. The sheet resistance of this sample was 1068 Q/#, which is comparable to low resistance GaN films grown at high temperature, which range from 100-500 Q/#. These results demonstrate the potential for LT Ill-nitrides in electronics applications. This work supported in part by Intel Corporation and the Solid State Lighting and Energy Electronics Center.

High to Ultrahigh Si-Doped GaN Grown by Metalorganic Chemical Vapor Deposition at 550 °C for Heterogeneous Integration

III nitride semiconductors have recently disrupted several industries and have remarkable potential to address unmet needs in electronics and optoelectronics. While gallium nitride (GaN) is the champion nitride material in solid state lighting and high power and high frequency electronics, there is abundant untapped potential in other nitrides that are otherwise harder to grow and to gain control over their electronic properties. Among these, Indium nitride (InN) that promises the highest saturation velocity in the nitride group poses two difficult challenges to realize its potential: (1) The epitaxial growth of high-quality InN films or structures is very challenging due to the competitive decomposition of InN at the temperatures for which efficient cracking of nitrogen sources occur, and (2) the difficulty in growing a larger bandgap barrier layer at the surface which requires even higher temperatures than the InN decomposition temperature, and with the absence of such layer, surface Fermi energy pinning challenges the modulation of the electron charge density to make functional transistor devices from any grown InN layers. Yes, there has been outstanding progress in the growth of InN layers by molecular beam epitaxy or plasma assisted metalorganic chemical vapor deposition (MOCVD), but the growth of smooth InN surfaces and the growth of larger barrier layers on InN has not been accomplished before: This work demonstrates by standard pulsed MOCVD growth the ability to grow defect free InN structures with smooth surfaces and the ability to grow with control GaN barrier layers and to demonstrate excellent transport characteristics in these structures. We hypothesized that coalescence of InN islands in constrained geometries such as lateral Fins can accelerate the formation of void-free and defect free InN growth within the first few nanometers of grown InN. We further hypothesized that we can raise the effective V/III ratio by pulsing the tri-methyl-indium source to avoid droplet formation, ripening and segregation which otherwise leads to the growth of defective and porous InN layers. We validated these hypotheses by studying growth parameters and Fin widths in the range of 60 nm to 2000 nm (and control planar samples) and demonstrated InN Fins with defect-free surfaces and single crystal structures. Unannealed Ti/Au metal contacts on packed InN Fin arrays resulted in effective (un-corrected) specific contact resistance of approximately 6Q¢um, which is much smaller than that obtained for current GaN ohmic contacts, with an extracted contact transfer length less than 1pm. To leverage these structures for high electron mobility applications and un-pin their surface Fermi energy, we successfully grew in-situ GaN/InN heterostructure without compromising the smooth InN surface. Transmission electron Microscopy showed clear interface between GaN and InN and single crystal structure. We then demonstrated that GaN can be selectively etched in the source/drain regions of the heterostructure and that unannealed Ti/Au metal contacts retain their low specific contact resistance on these structures. We are now investigating the fabrication of GaN/InN and AIN/INN HEMTs and their DC/RF performance.

Demonstration of Single Crystal InN & GaN/InN Heterostructures by MOCVD

Nanoscale spintronics devices can revolutionize computer logic and memory units. Interestingly, paramagnetic nanostructures strongly exchange coupled with two ferromagnetic electrodes can yield novel forms of magnetic materials. However, there is a knowledge gap about the role of the number of paramagnetic nanostructures on the various properties of whole spintronics devices. To make this study relevant to the experimentally attainable device structure, we focus on the magnetic tunnel junction (MTJ) based spintronics device architecture. Under this approach, paramagnetic nanostructures are placed along the MTJ perimeter. We assume that the tunnel barrier of the MTJ does not allow any leakage current or exchange coupling, and paramagnetic nanostructures dictate the exchange coupling between the ferromagnetic electrodes. Also, the width of the ferromagnetic electrodes is governed by the number of paramagnetic nanostructures. This study systematically varied the number of nanostructures from 1 to 625 (25 x 25). The overall device was represented by a Heisenberg 3D model containing five atomic layer thick ferromagnetic electrodes. The number of paramagnetic nanostructures governed the width of the ferromagnetic electrodes. For instance, the device with a single nanostructure and 5 x 5 nanostructure possessed FM electrodes with one atom and five atom width, respectively. The paramagnetic nanostructures — sandwiched between the two FM electrodes — were placed on the perimeter of the 5 x 5 square with an empty space inside the square. The empty space shows the presence of an insulating spacer needed to provide the physical separation to enable paramagnetic nanostructures to control the spin dynamics of the device . The strength of exchange coupling between the paramagnetic nanostructure and ferromagnetic electrodes was fixed to be antiferromagnetic, consistent with experimental observations with analogous devices . We observed that thermal energy strongly influenced the temporal evolution of the equilibrium state of devices. The device with a single paramagnetic nanostructure struggled to align the left ferromagnet (Left-FM) and right ferromagnetic electrode (Right -FM) at low thermal energy of kT = 0.01. At higher thermal energy, devices with a single paramagnetic nanostructure underwent significant fluctuations. The device with a 5 x 5 paramagnetic structure also had difficulty attaining the fully antiparallel state at low thermal energy of kT = 0.01. However, at higher thermal energy of kT = 0.1, 5 x 5 paramagnetic nanostructure started producing conclusive antiparallel ferromagnetic electrodes. This paper will discuss the full range of paramagnetic nanostructures up to 25 x 25 sizes over the thermal energy range from 0.01 to 0.1. To estimate the spatial impact range of the nanostructures, we also investigated the spatial correlation factor for each case. In addition, we also compute the spatial magnetic susceptibility and heat capacity of the device. References: 1. Tyagi, P.; Riso, C.; Friebe, E., Magnetic Tunnel Junction Based Molecular Spintronics Devices Exhibiting Current Suppression At Room Temperature. Organic Electronics 2019, 64, 188-194. 2. Savadkoohi, M.; Dahal, B. R.; Grizzle, A.; D'Angelo, C.; Tyagi, P., Interaction between magnetic molecules and two ferromagnetic electrodes of a magnetic tunnel junction (MTJ). Journal of Magnetism and Magnetic Materials 2021, 529, 167902.

A Monte Carlo Study of Paramagnetic Nanostructure Coupled with Two Ferromagnetic Electrodes of a Cross-Junction Shaped Spintronics Device at Different Thermal Energies

When paramagnetic molecules covalently bond to a ferromagnet (FM), they undergo extensive hybridization with the surface and result in a spin-polarized molecule-ferromagnet interface. The resulting ferromagnet-molecule hybridization leads to a wide range of active functionalities, such as energy-level control and spin filtering capabilities . Magnetic tunnel junction-based molecular spintronics devices (MTJMSDs) are fabricated by bridging monolayers of molecules across the MTU's tunnel barrier, where they chemically bond with the FM electrodes. Thus, MTJMSDs become a highly promising testbed for controlled spintronics at room temperature MTJMSD testbed also allows the molecule-ferromagnet interface to become a significant spin pathway enabling new equilibrium density of states over long range’ ”’ Understanding the role of spin fluctuations in MTJMSD with various types of metallic electrodes is exceptionally challenging. We conducted theoretical studies to understand the free electrons spin effect on MTJMSD magnetization using 3D Heisenberg-based Monte Carlo simulations. For this study, we varied the electron spin in 1) ferromagnetferromagnet, 2) ferromagnet-paramagnet, and 3) ferromagnet-antiferromagnet electrode pairs. In general, we found that as the magnitude of free electrons spin in the electrodes and molecules increased, the device magnetization increased when the free electron had parallel coupling with its host atom. Conversely, the total device magnetization decreased for antiparallel electron-atom coupling. Interestingly, long-range ordering in antiferromagnetic electrodes diminished with antiparallel electron-atom coupling and was enhanced with parallel coupling for a free-electron spin of equal magnitude at room temperature. In this study, we also recorded the correlated distribution of the devices’ magnetic moment to elucidate the spatial impact range of molecules as a function of free electron spin. We also explored the electron spin effect on magnetic susceptibility and heat capacity. This research may inform the designing of novel molecular spintronics devices by providing a knowledge base about the impact of free electron spin for varying electrode materials. This research is supported by National Science Foundation-CREST Award (Contract # HRD- 1914751), Department of Energy/ National Nuclear Security Agency (DE-FOA-0003945). 1. A. Cornia and P. Seneor, Nature Materials 16 (5), 505-506 (2017). 2. P. Tyagi, C. Riso, U. Amir, C. Rojas-Dotti and J. Martinez-Lillo, RSC Advances 10 (22), 13006-13015 (2020). 3. P. Tyagi, C. Riso and E. Friebe, Organic Electronics 64, 188-194 (2019).

Spin Fluctuation Effect on Magnetic Tunnel Junction-Based Molecular Spintronics Devices (MTJMSD)

High-performance thermoelectric materials are currently being sought after to recycle waste heat. Copper chalcogenides in general are materials of great interest because of their naturally low thermal conductivity and readily modifiable electronic properties. The compounds Cu5Sn2Q7 were previously reported to have metal-like properties, which is not a desirable characteristic for thermoelectric materials. The aim of this study was to reduce the carrier concentration of these materials by Zn-doping, and then investigate the electronic and thermoelectric properties of the doped materials in comparison to the undoped ones. The compounds were synthesized using both the traditional solid-state tube method and ball-milling. The crystal structures were characterized using powder X-ray diffraction, which confirmed that all materials crystallize in the monoclinic system with the space group C2. With the partial substitution of zinc for copper atoms, the compounds exhibited an overall improvement in their thermoelectric properties. Figure of merit values were determined to be 0.20 for Cu4ZnSn2Se7 at 615 K and 0.05 for Cu4ZnSn2Te7 at 575 K

Zinc Multi-Pnictogens Semiconductors—Cu Doping and Thermoelectric Characteristics

Boron nitride (BN) nanotube is an anisotropic nanomaterial that possess unique intrinsic properties like high thermal conductivity, electrically insulating, high oxidation resistance, superior mechanical strength, and piezoelectric property. The incorporation of the BN nanotubes in polymer has created opportunities to produce composites with a wide range of possible applications like aerospace applications, thermal interface material. However, the improved properties of these composite like thermal transport ability are still far from expected and theoretical stipulations due to the random orientation of these nanotubes with excellent in-plane properties and poor out-of-plane properties. Therefore, controlling the orientation of the nanotubes in the composite is important for optimizing its performance. This paper focused on the magnetic modification of boron nitride nanotubes for their alignment in polymer composite. The magnetic modification of the BN nanotube is carried out by functionalizing nanotubes with iron oxide nanoparticles (magnetite) which produces paramagnetic BN nanotubes. These functionalized BN nanotubes exhibit magnetic responses that can enable control over their orientation and position under low external magnetic fields in low viscous fluids. The BN nanotubes are modified through electrostatic interaction with the iron oxide nanoparticles, therefore, preserving their intrinsic properties and structure. The paramagnetic nanotubes are to be dispersed in polymer fluid, controlled with magnets, and cured to maintain nanotubes' position and alignment. The magnetic functionalization of BN nanotubes can provide the ability to spatially manipulate these nanotubes into more complex networks crucial for applications in nanoelectronics, sensors, spintronics, and thermoelectric devices. It can also enable the fabrication of anisotropic composite materials with improved directional property and high thermal transport ability.

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Facile Integration of Giant Exchange Bias in 2D Magnet/Oxide Heterostructures

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Fast and Easy Optical Imaging and Epitaxial Growth Control of Rotational Domains in SnSe Thin Films

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