8 research outputs found
Structure, Stability, and Properties of the Intergrowth Compounds ([SnSe]<sub>1+δ</sub>)<sub><i>m</i></sub>(NbSe<sub>2</sub>)<sub><i>n</i></sub>, where <i>m</i> = <i>n</i> = 1–20
Intergrowth
compounds of ([SnSe]<sub>1+δ</sub>)<sub><i>m</i></sub>(NbSe<sub>2</sub>)<sub><i>n</i></sub>,
where 1 ≤ <i>m = n ≤ </i>20, with the same
atomic composition but different <i>c</i>-axis lattice parameters
and number of interfaces per volume were synthesized using the modulated
elemental reactant technique. A <i>c</i>-axis lattice parameter
change of 1.217(6) nm as a function of one unit of <i>m</i> = <i>n</i> was observed. In-plane X-ray diffraction shows
an increase in distortion of the rock salt layer as a function of <i>m</i> and a broadening of the NbSe<sub>2</sub> reflections as <i>n</i> increases, indicating the presence of different coordination
environments for Nb (trigonal prismatic and octahedral) and smaller
crystallite size, which were confirmed via scanning transmission electron
microscopy investigations. The electrical resistivities of all 12
compounds exhibit metallic temperature dependence and are similar
in magnitude as would be expected for isocompositional compounds.
Carrier concentration and mobility of the compounds vary within a
narrow range of 2–6 × 10<sup>21</sup> cm<sup>–3</sup> and 2–6 cm<sup>2</sup> V<sup>–1</sup> s<sup>–1</sup>, respectively. Even at a thickness of 12 nm for the SnSe and NbSe<sub>2</sub> blocks, the properties of the intergrowth compounds cannot
be explained as composite behavior, due to significant charge transfer
between them. Upon being annealed at 500 °C, the higher order <i>m</i> = <i>n</i> compounds were found to convert to
the thermodynamically stable phase, the (1,1) compound. This suggests
that the capacitive energy of the interfaces stabilizes these intergrowth
compounds
Effect of Local Structure of NbSe<sub>2</sub> on the Transport Properties of ([SnSe]<sub>1.16</sub>)<sub>1</sub>(NbSe<sub>2</sub>)<sub><i>n</i></sub> Ferecrystals
([SnSe]<sub>1.16</sub>)<sub>1</sub>(NbSe<sub>2</sub>)<sub><i>n</i></sub> ferecrystals were
synthesized through the modulated
elemental reactants technique by increasing the number of Nb|Se layers
in the precursor from 1 to 4. The <i>c</i>-lattice parameter
of the intergrowth was observed to change as a function of <i>n</i> by 0.635(2) nm. The <i>c</i>-lattice parameter
of SnSe was observed to be 0.588(8) nm and independent of <i>n</i>. The electrical resistivity does not decrease as <i>n</i> increases as expected from simple models, but instead
the trend in the resistivity is (1,3) > (1,4) ≥ (1,1) >
(1,2).
The carrier concentration increases with <i>n</i> as expected,
so the unusual trend in resistivity is a result of the carrier mobility
decreasing with increasing <i>n.</i> In-plane X-ray diffraction
line widths and STEM images of the (1,4) compound show that it has
small in-plane grain sizes and a large diversity of stacking sequences
respectively, providing a potential explanation for the reduced carrier
mobility
The Influence of Interfaces on Properties of Thin-Film Inorganic Structural Isomers Containing SnSe–NbSe<sub>2</sub> Subunits
Inorganic isomers ([SnSe]<sub>1+δ</sub>)<sub><i>m</i></sub>(NbSe<sub>2</sub>)<sub><i>n</i></sub>([SnSe]<sub>1+δ</sub>)<sub><i>p</i></sub>(NbSe<sub>2</sub>)<sub><i>q</i></sub>([SnSe]<sub>1+δ</sub>)<sub><i>r</i></sub>(NbSe<sub>2</sub>)<sub><i>s</i></sub> where <i>m</i>, <i>n</i>, <i>p</i>, <i>q</i>, <i>r</i>, and <i>s</i> are integers and <i>m</i> + <i>p</i> + <i>r</i> = <i>n</i> + <i>q</i> + <i>s</i> = 4 were prepared using the modulated elemental reactant technique. This series of all six possible isomers provides an opportunity to study the influence of interface density on properties while maintaining the same unit cell size and composition. As expected, all six compounds were observed to have the same atomic compositions and an almost constant <i>c</i>-axis lattice parameter of ≈4.90(5) nm, with a slight trend in the <i>c</i>-axis lattice parameter correlated with the different number of interfaces in the isomers: two, four and six. The structures of the constituents in the <i>ab</i>-plane were independent of one another, confirming the nonepitaxial relationship between them. The temperature dependent electrical resistivities revealed metallic behavior for all the six compounds. Surprisingly, the electrical resistivity at room temperature decreases with increasing number of interfaces. Hall measurements suggest this results from changes in carrier concentration, which increases with increasing thickness of the thickest SnSe block in the isomer. Carrier mobility scales with the thickness of the thickest NbSe<sub>2</sub> block due to increased interfacial scattering as the NbSe<sub>2</sub> blocks become thinner. The observed behavior suggests that the two constituents serve different purposes with respect to electrical transport. SnSe acts as a charge donor and NbSe<sub>2</sub> acts as the charge transport layer. This separation of function suggests that such heterostructures can be designed to optimize performance through choice of constituent, layer thickness, and layer sequence. A simplistic model, which predicts the properties of the complex isomers from a weighted sum of the properties of building blocks, was developed. A theoretical model is needed to predict the optimal compound for specific properties among the many potential compounds that can be prepared
Suppressing a Charge Density Wave by Changing Dimensionality in the Ferecrystalline Compounds ([SnSe]<sub>1.15</sub>)<sub>1</sub>(VSe<sub>2</sub>)<sub><i>n</i></sub> with <i>n</i> = 1, 2, 3, 4
The compounds, ([SnSe]<sub>1.15</sub>)<sub>1</sub>(VSe<sub>2</sub>)<sub><i>n</i></sub> with <i>n</i> = 1, 2, 3,
and 4, were prepared using designed precursors in order to investigate
the influence of the thickness of the VSe<sub>2</sub> constituent
on the charge density wave transition. The structure of each of the
compounds was determined using X-ray diffraction and scanning transmission
electron microscopy. The charge density wave transition observed in
the resistivity of ([SnSe]<sub>1.15</sub>)<sub>1</sub>(VSe<sub>2</sub>)<sub>1</sub> was confirmed. The electrical properties of the <i>n</i> = 2 and 3 compounds are distinctly different. The magnitude
of the resistivity change at the transition temperature is dramatically
lowered and the temperature of the resistivity minimum systematically
increases from 118 K (<i>n</i> = 1) to 172 K (<i>n</i> = 3). For <i>n</i> = 1, this temperature correlates with
the onset of the charge density wave transition. The Hall-coefficient
changes sign when <i>n</i> is greater than 1, and the temperature
dependence of the Hall coefficient of the <i>n</i> = 2 and
3 compounds is very similar to the bulk, slowly decreasing as the
temperature is decreased, while for the <i>n</i> = 1 compound
the Hall coefficient increases dramatically starting at the onset
of the charge density wave. The transport properties suggest an abrupt
change in electronic properties on increasing the thickness of the
VSe<sub>2</sub> layer beyond a single layer
Charge Density Wave Transition in (PbSe)<sub>1+δ</sub>(VSe<sub>2</sub>)<sub><i>n</i></sub> Compounds with <i>n</i> = 1, 2, and 3
A series
of (PbSe)<sub>1+δ</sub>(VSe<sub>2</sub>)<sub><i>n</i></sub> heterostructures with extensive turbostratic disorder were
synthesized with <i>n</i> = 1–3 through low temperature
annealing of appropriately designed layered precursors. The crystal
structures consist of alternating layers of CdI<sub>2</sub> type structured
VSe<sub>2</sub> and distorted NaCl type structured PbSe. The <i>n</i> = 1 compound has a positive Hall coefficient and a charge
density wave like transition at 100 K, during which the resistivity
increases by a factor of 3.5 and the Hall coefficient increases by
a factor of 8. The <i>n</i> = 2 and 3 compounds have negative
Hall coefficients and significantly smaller changes in the slope of
the resistivity and Hall coefficient as a function of temperature
at similar temperatures. The distinctly different transport properties
of the compound containing a monolayer of VSe<sub>2</sub> compared
to compounds with thicker VSe<sub>2</sub> layers highlights the complexity
of the electronic structure of these stacked systems. The differences
cannot be simply explained by charge transfer between VSe<sub>2</sub> and PbSe within a rigid band model. More sophisticated interactions
between the constituent layers, electron–phonon interactions,
and/or correlation between electrons need to be considered to explain
the change in carrier type and the charge density wave (CDW) transition
Tuning Electrical Properties through Control of TiSe<sub>2</sub> Thickness in (BiSe)<sub>1+δ</sub>(TiSe<sub>2</sub>)<sub><i>n</i></sub> Compounds
A series of (BiSe)<sub>1+δ</sub>(TiSe<sub>2</sub>)<sub><i>n</i></sub> compounds where <i>n</i> was varied from
two to four were synthesized and electrically characterized to explore
the extent of charge transfer from the BiSe layer to the TiSe<sub>2</sub> layers. These kinetically stable heterostructures were prepared
using the modulated elemental reactants (MER) method, in which thin
amorphous elemental layers are deposited in an order that mimics the
nanostructure of the desired product. X-ray diffraction (XRD), X-ray
area diffraction, and scanning transmission electron microscopy (STEM)
data show that the precursors formed the desired products. Specular
diffraction scans contain only 00<i>l</i> reflections, indicating
that the compounds are crystallographically aligned with the <i>c</i>-axis perpendicular to the substrate. The <i>c</i>-axis lattice parameter increases by 0.604(3) nm with each additional
TiSe<sub>2</sub> layer. In-plane diffraction scans contain reflections
that can be indexed as the (<i>hk</i>0) of the BiSe and
TiSe<sub>2</sub> constituents. Area diffraction scans are also consistent
with the samples containing only BiSe and TiSe<sub>2</sub> constituents.
Rietveld refinement of the 00<i>l</i> XRD data was used
to determine the positions of atomic planes along the <i>c</i>-axis. STEM data supports the structures suggested by the diffraction
data and associated refinements but also shows that antiphase boundaries
occur approximately 1/3 of the time in the BiSe layers. All samples
showed metallic behavior for the temperature-dependent electrical
resistivity between 20 K and room temperature. Electrical measurements
indicated that charge is transferred from the BiSe layer to the TiSe<sub>2</sub> layer. The measured Hall coefficients were all negative indicating
that electrons are the majority carrier and are systematically decreased
as <i>n</i> was increased. Assuming a single parabolic band
model, carrier concentration decreased when the number of TiSe<sub>2</sub> layers is increased, suggesting that the amount of charge
donated by the BiSe layer to the TiSe<sub>2</sub> layers is constant.
Seebeck coefficients were negative for all of the (BiSe)<sub>1+δ</sub>(TiSe<sub>2</sub>)<sub><i>n</i></sub> compounds studied,
indicating that electrons are the majority carrier, and decreased
as <i>n</i> increased. The effective mass of the carriers
was calculated to be 5–6 m<sub>e</sub> for the series of compounds
Expanding the Concept of van der Waals Heterostructures to Interwoven 3D Structures
Several members of
a new family of heterostructures [(LaSe)<sub>1.17</sub>]<sub>1</sub>V<sub><i>n</i>(1+<i>y</i>)+1</sub>Se<sub>2<i>n</i>+2</sub> with <i>n</i> = 1, 2, and 3 were prepared
using a diffusion constrained, kinetically
controlled synthesis approach. Specular diffraction patterns collected
as a function of annealing temperature show the evolution of designed
precursors into highly ordered heterostructures. Scanning transmission
electron microscopy (STEM) images reveal that the structure of <i>n</i> = 3 consists of rock salt structured LaSe bilayers alternating
with vanadium selenide layers of varying thickness, which are structurally
closely related to V<sub>3</sub>Se<sub>4</sub>. Interplanar distances
obtained from the STEM images were successfully used as the starting
point for Rietveld refinements of the specular diffraction patterns
of these crystallographically aligned compounds. Utilizing this unorthodox
combined approach to extract detailed structural information unambiguously,
we demonstrated that these thin film compounds are the first examples
of chalcogenide-based heterostructures, where the bulk structures
of both building blocks lack a van der Waals gap, yet a nonepitaxial
incommensurate interface forms. Moreover, the refinement results of
the <i>n</i> = 2 and 3 heterostructures suggest that the
structure of the V–Se layers can be varied ranging from VSe<sub>2</sub> to VSe depending on the film composition. The electrical
resistivity of the [(LaSe)<sub>1.17</sub>]<sub>1</sub>V<sub><i>n</i>(1+<i>y</i>)+1</sub>Se<sub>2<i>n</i>+2</sub> heterostructures changes systematically from semiconducting
toward metallic behavior with increasing <i>n</i>, showcasing
the ability to tune physical properties by precisely controlling the
layer sequence in these heterostructures
BaTiO<sub>3</sub> Thin Films from Atomic Layer Deposition: A Superlattice Approach
A superlattice
approach for the atomic layer deposition of polycrystalline
BaTiO<sub>3</sub> thin films is presented as an example for an effective
route to produce high-quality complex oxide films with excellent thickness
and compositional control. This method effectively mitigates any undesirable
reactions between the different precursors and allows an individual
optimization of the reaction conditions for the Ba–O and the
Ti–O subcycles. By growth of nanometer thick alternating BaÂ(OH)<sub>2</sub> and TiO<sub>2</sub> layers, the advantages of binary oxide
atomic layer deposition are transferred into the synthesis of ternary
compounds, permitting extremely high control of the cation ratio and
superior uniformity. Whereas the BaÂ(OH)<sub>2</sub> layers are partially
crystalline after the deposition, the TiO<sub>2</sub> layers remain
mostly amorphous. The layers react to polycrystalline, polymorph BaTiO<sub>3</sub> above 500 °C, releasing H<sub>2</sub>O. This solid-state
reaction is accompanied by an abrupt decrease in film thickness. Transmission
electron microscopy and Raman spectroscopy reveal the presence of
hexagonal BaTiO<sub>3</sub> in addition to the perovskite phase in
the annealed films. The microstructure with relatively small grains
of ∼70 Å and different phases is a direct consequence
of the abrupt formation reaction. The electrical properties transition
from the initially highly insulating dielectric semiamorphous superlattice
into a polycrystalline BaTiO<sub>3</sub> thin film with a dielectric
constant of 117 and a dielectric loss of 0.001 at 1 MHz after annealing
at 600 °C in air, which, together with the suppression of ferroelectricity
at room temperature, are very appealing properties for voltage tunable
devices