15 research outputs found
Ba<sub>2</sub>HgS<sub>5</sub>A Molecular Trisulfide Salt with Dumbbell-like (HgS<sub>2</sub>)<sup>2–</sup> Ions
Ba<sub>2</sub>HgS<sub>5</sub> was synthesized by cooling a molten
mixture of BaS, HgS, and elemental sulfur. It crystallizes in the
orthorhombic <i>Pnma</i> space group with <i>a</i> = 12.190(2) Å, <i>b</i> = 8.677(2) Å, <i>c</i> = 8.371(2) Å, and <i>d</i><sub>calc</sub> = 4.77 g cm<sup>–3</sup>. Its crystal structure consists
of isolated dumbbell-shaped (HgS<sub>2</sub>)<sup>2–</sup> and
v-shaped S<sub>3</sub><sup>2–</sup> ions. These molecular anions
are charge-balanced by Ba<sup>2+</sup> cations. Raman spectroscopy
shows three strong bands originating from symmetric, asymmetric, and
bending vibrational modes of the S<sub>3</sub><sup>2–</sup> ions. X-ray photoelectron spectroscopic analysis confirms the presence
of the trisulfide species. Ba<sub>2</sub>HgS<sub>5</sub> has a bandgap
of ∼2.4 eV. Electronic band structure calculations show that
the bandgap is defined essentially by the p-orbitals of the sulfur
atoms of the S<sub>3</sub><sup>2–</sup> group
Antagonism between Spin–Orbit Coupling and Steric Effects Causes Anomalous Band Gap Evolution in the Perovskite Photovoltaic Materials CH<sub>3</sub>NH<sub>3</sub>Sn<sub>1–<i>x</i></sub>Pb<sub><i>x</i></sub>I<sub>3</sub>
Halide perovskite solar cells are
a recent ground-breaking development
achieving power conversion efficiencies exceeding 18%. This has become
possible owing to the remarkable properties of the AMX<sub>3</sub> perovskites, which exhibit unique semiconducting properties. The
most efficient solar cells utilize the CH<sub>3</sub>NH<sub>3</sub>PbI<sub>3</sub> perovskite whose band gap, <i>E</i><sub>g</sub>, is 1.55 eV. Even higher efficiencies are anticipated, however,
if the band gap of the perovskite can be pushed deeper in the near-infrared
region, as in the case of CH<sub>3</sub>NH<sub>3</sub>SnI<sub>3</sub> (<i>E</i><sub>g</sub> = 1.3 eV). A remarkable way to improve
further comes from the CH<sub>3</sub>NH<sub>3</sub>Sn<sub>1–<i>x</i></sub>Pb<sub><i>x</i></sub>I<sub>3</sub> solid
solution, which displays an anomalous trend in the evolution of the
band gap with the compositions approaching <i>x</i> = 0.5
displaying lower band gaps (<i>E</i><sub>g</sub> ≈
1.1 eV) than that of the lowest of the end member, CH<sub>3</sub>NH<sub>3</sub>SnI<sub>3</sub>. Here we use first-principles calculations
to show that the competition between the spin–orbit coupling
(SOC) and the lattice distortion is responsible for the anomalous
behavior of the band gap in CH<sub>3</sub>NH<sub>3</sub>Sn<sub>1–<i>x</i></sub>Pb<sub><i>x</i></sub>I<sub>3</sub>. SOC
causes a linear reduction as <i>x</i> increases, while the
lattice distortion causes a nonlinear increase due to a composition-induced
phase transition near <i>x</i> = 0.5. Our results suggest
that electronic structure engineering can have a crucial role in optimizing
the photovoltaic performance
Semiconducting [(Bi<sub>4</sub>Te<sub>4</sub>Br<sub>2</sub>)(Al<sub>2</sub>Cl<sub>6–<i>x</i></sub>Br<sub><i>x</i></sub>)]Cl<sub>2</sub> and [Bi<sub>2</sub>Se<sub>2</sub>Br](AlCl<sub>4</sub>): Cationic Chalcogenide Frameworks from Lewis Acidic Ionic Liquids
Lewis
acidic organic ionic liquids provide a novel synthetic medium to prepare
new semiconducting chalcogenides, [(Bi<sub>4</sub>Te<sub>4</sub>Br<sub>2</sub>)Â(Al<sub>2</sub>Cl<sub>5.46</sub>Br<sub>0.54</sub>)]ÂCl<sub>2</sub> (<b>1</b>) and [Bi<sub>2</sub>Se<sub>2</sub>Br]Â(AlCl<sub>4</sub>) (<b>2</b>). Compound <b>1</b> features a cationic
[(Bi<sub>4</sub>Te<sub>4</sub>Br<sub>2</sub>)Â(Al<sub>2</sub>Cl<sub>5.46</sub>Br<sub>0.54</sub>)]<sup>2+</sup> three-dimensional framework,
while compound <b>2</b> consists of cationic layers of [Bi<sub>2</sub>Se<sub>2</sub>Br]<sup>2+</sup>. Spectroscopically measured
band gaps of <b>1</b> and <b>2</b> are ∼0.6 and
∼1.2 eV, respectively. Thermoelectric power measurements of
single crystals of <b>1</b> indicate an n-type semiconductor
Possible <i>n–</i>type carrier sources in In<sub>2</sub>O<sub>3</sub>(ZnO)<sub>k</sub>
Homologous compounds with the formula In<sub>2</sub>O<sub>3</sub>(ZnO)<sub>k</sub>, where k is an integer, have potential applications
as transparent conducting oxides and high temperature thermoelectric
materials. In this study, we focus on the defect properties. Using
the <i>k</i> = 3 phase as a prototype, we calculate with
the first-principles
method the defect formation energies and transition levels of the
most probable <i>n</i>-type carrier producers,
which include oxygen vacancy (V<sub>O</sub>), indium antisite on zinc
(In<sub>Zn</sub>), indium interstitial (In<sub>i</sub>), and zinc
interstitial (Zn<sub>i</sub>). The site-preference of these defects
has been explored by comparing the total energies of defects at different
sites. Under the <i>n</i>-type environment, In<sub>Zn</sub> has a low formation energy and meanwhile a transition energy level
close to the conduction band minimum (CBM); V<sub>O</sub> also has
a lower formation energy, however a deep transition energy level in
the band gap; the cation interstitials have high formation energies,
although their defect transition energy levels are quite shallow.
Besides, we find that V<sub>O</sub> and In<sub>Zn</sub> tend to form
a defect complex when the two isolated defects take the nearest-neighboring
atomic sites in the same <i>ab</i>-plane. We conclude that
In<sub>Zn</sub> and its related defect-complex are the possible <i>n</i>–type carrier sources in In<sub>2</sub>O<sub>3</sub>(ZnO)<sub>k</sub>. Besides, we found that V<sub>O</sub> has
a significant site-preference, which can modify the site-preference
of In<sub>Zn</sub> by forming defect-complexes. This may lead to high
anisotropy in relaxation time, and then the experimentally reported
strong anisotropy in electrical conductivities in In<sub>2</sub>O<sub>3</sub>(ZnO)<sub>5</sub>
Semiconducting [(Bi<sub>4</sub>Te<sub>4</sub>Br<sub>2</sub>)(Al<sub>2</sub>Cl<sub>6–<i>x</i></sub>Br<sub><i>x</i></sub>)]Cl<sub>2</sub> and [Bi<sub>2</sub>Se<sub>2</sub>Br](AlCl<sub>4</sub>): Cationic Chalcogenide Frameworks from Lewis Acidic Ionic Liquids
Lewis
acidic organic ionic liquids provide a novel synthetic medium to prepare
new semiconducting chalcogenides, [(Bi<sub>4</sub>Te<sub>4</sub>Br<sub>2</sub>)Â(Al<sub>2</sub>Cl<sub>5.46</sub>Br<sub>0.54</sub>)]ÂCl<sub>2</sub> (<b>1</b>) and [Bi<sub>2</sub>Se<sub>2</sub>Br]Â(AlCl<sub>4</sub>) (<b>2</b>). Compound <b>1</b> features a cationic
[(Bi<sub>4</sub>Te<sub>4</sub>Br<sub>2</sub>)Â(Al<sub>2</sub>Cl<sub>5.46</sub>Br<sub>0.54</sub>)]<sup>2+</sup> three-dimensional framework,
while compound <b>2</b> consists of cationic layers of [Bi<sub>2</sub>Se<sub>2</sub>Br]<sup>2+</sup>. Spectroscopically measured
band gaps of <b>1</b> and <b>2</b> are ∼0.6 and
∼1.2 eV, respectively. Thermoelectric power measurements of
single crystals of <b>1</b> indicate an n-type semiconductor
LiPbSb<sub>3</sub>S<sub>6</sub>: A Semiconducting Sulfosalt with Very Low Thermal Conductivity
The
new semiconductor LiPbSb<sub>3</sub>S<sub>6</sub> crystallizes in
the space group <i>P</i>2<sub>1</sub>/<i>c</i>. The structure is a member of the lillianite homologous series and
is composed of layers of PbS archetype Sb/Li–S separated by
trigonal-prismatic-coordinated Pb/Li. Electronic band structure calculations
indicate an indirect band gap, with direct gaps lying very close in
energy. LiPbSb<sub>3</sub>S<sub>6</sub> has one of the lowest thermal
conductivities seen in a crystalline material, ∼0.24 W m<sup>–1</sup> K<sup>–1</sup> at room temperature, and a
high resistivity, ∼4 × 10<sup>9</sup> Ω·cm,
and exhibits strong light absorption with a nearly direct band gap
of 1.6 eV
LiPbSb<sub>3</sub>S<sub>6</sub>: A Semiconducting Sulfosalt with Very Low Thermal Conductivity
The
new semiconductor LiPbSb<sub>3</sub>S<sub>6</sub> crystallizes in
the space group <i>P</i>2<sub>1</sub>/<i>c</i>. The structure is a member of the lillianite homologous series and
is composed of layers of PbS archetype Sb/Li–S separated by
trigonal-prismatic-coordinated Pb/Li. Electronic band structure calculations
indicate an indirect band gap, with direct gaps lying very close in
energy. LiPbSb<sub>3</sub>S<sub>6</sub> has one of the lowest thermal
conductivities seen in a crystalline material, ∼0.24 W m<sup>–1</sup> K<sup>–1</sup> at room temperature, and a
high resistivity, ∼4 × 10<sup>9</sup> Ω·cm,
and exhibits strong light absorption with a nearly direct band gap
of 1.6 eV
An Unusual Crystal Growth Method of the Chalcohalide Semiconductor, β‑Hg<sub>3</sub>S<sub>2</sub>Cl<sub>2</sub>: A New Candidate for Hard Radiation Detection
We assess the mercury
chalcohalide compound, β-Hg<sub>3</sub>S<sub>2</sub>Cl<sub>2</sub>, as a potential semiconductor material
for X-ray and γ-ray detection. It has a high density (6.80 g/cm<sup>3</sup>) and wide band gap (2.56 eV) and crystallizes in the cubic <i>Pm</i>3̅<i>n</i> space group with a three-dimensional
structure comprised of [Hg<sub>12</sub>S<sub>8</sub>] cubes with Cl
atoms located within and between the cubes, featuring a trigonal pyramidal
SHg<sub>3</sub> as the main building block. First-principle electronic
structure calculations at the density functional theory level predict
that the compound has closely lying indirect and direct band gaps.
We have successfully grown transparent, single crystals of β-Hg<sub>3</sub>S<sub>2</sub>Cl<sub>2</sub> up to 7 mm diameter and 1 cm long
using a new approach by the partial decomposition of the quaternary
Hg<sub>3</sub>Bi<sub>2</sub>S<sub>2</sub>Cl<sub>8</sub> compound followed
by the formation of β-Hg<sub>3</sub>S<sub>2</sub>Cl<sub>2</sub> and an impermeable top layer, all happening in situ during vertical
Bridgman growth. The decomposition process was optimized by varying
peak temperatures and temperature gradients using a 2 mm/h translation
rate of the Bridgman technique. Formation of the quaternary Hg<sub>3</sub>Bi<sub>2</sub>S<sub>2</sub>Cl<sub>8</sub> followed by its
partial decomposition into β-Hg<sub>3</sub>S<sub>2</sub>Cl<sub>2</sub> was confirmed by in situ temperature-dependent synchrotron
powder diffraction studies. The single crystal samples obtained had
resistivity of 10<sup>10</sup> Ω·cm and mobility-lifetime
products of electron and hole carriers of 1.4(4) × 10<sup>–4</sup> cm<sup>2</sup>/V and 7.5(3) × 10<sup>–5</sup> cm<sup>2</sup>/V, respectively. Further, an appreciable Ag X-ray photoconductivity
response was observed showing the potential of β-Hg<sub>3</sub>S<sub>2</sub>Cl<sub>2</sub> as a hard radiation detector material
CsSnI<sub>3</sub>: Semiconductor or Metal? High Electrical Conductivity and Strong Near-Infrared Photoluminescence from a Single Material. High Hole Mobility and Phase-Transitions
CsSnI<sub>3</sub> is an unusual perovskite that undergoes
complex
displacive and reconstructive phase transitions and exhibits near-infrared
emission at room temperature. Experimental and theoretical studies
of CsSnI<sub>3</sub> have been limited by the lack of detailed crystal
structure characterization and chemical instability. Here we describe
the synthesis of pure polymorphic crystals, the preparation of large
crack-/bubble-free ingots, the refined single-crystal structures,
and temperature-dependent charge transport and optical properties
of CsSnI<sub>3</sub>, coupled with <i>ab initio</i> first-principles
density functional theory (DFT) calculations. <i>In situ</i> temperature-dependent single-crystal and synchrotron powder X-ray
diffraction studies reveal the origin of polymorphous phase transitions
of CsSnI<sub>3</sub>. The black orthorhombic form of CsSnI<sub>3</sub> demonstrates one of the largest volumetric thermal expansion coefficients
for inorganic solids. Electrical conductivity, Hall effect, and thermopower
measurements on it show p-type metallic behavior with low carrier
density, despite the optical band gap of 1.3 eV. Hall effect measurements
of the black orthorhombic perovskite phase of CsSnI<sub>3</sub> indicate
that it is a p-type direct band gap semiconductor with carrier concentration
at room temperature of ∼ 10<sup>17</sup> cm<sup>–3</sup> and a hole mobility of ∼585 cm<sup>2</sup> V<sup>–1</sup> s<sup>–1</sup>. The hole mobility is one of the highest observed
among p-type semiconductors with comparable band gaps. Its powders
exhibit a strong room-temperature near-IR emission spectrum at 950
nm. Remarkably, the values of the electrical conductivity and photoluminescence
intensity increase with heat treatment. The DFT calculations show
that the screened-exchange local density approximation-derived band
gap agrees well with the experimentally measured band gap. Calculations
of the formation energy of defects strongly suggest that the electrical
and light emission properties possibly result from Sn defects in the
crystal structure, which arise intrinsically. Thus, although stoichiometric
CsSnI<sub>3</sub> is a semiconductor, the material is prone to intrinsic
defects associated with Sn vacancies. This creates highly mobile holes
which cause the materials to appear metallic
Cs<sub>2</sub>M<sup>II</sup>M<sup>IV</sup><sub>3</sub>Q<sub>8</sub> (Q = S, Se, Te): An Extensive Family of Layered Semiconductors with Diverse Band Gaps
Flame-melting rapid-cooling reactions
were used to synthesize a
number of pure phases of the Cs<sub>2</sub>M<sup>II</sup>M<sup>IV</sup><sub>3</sub>Q<sub>8</sub> family (M<sup>II</sup> = Mg, Zn, Cd, Hg;
M<sup>IV</sup> = Ge, Sn; Q = S, Se, Te) whereas the more toxic members
were synthesized using a traditional tube furnace synthesis. All Cs<sub>2</sub>M<sup>II</sup>M<sup>IV</sup><sub>3</sub>Q<sub>8</sub> compounds
presented here crystallize in the noncentrosymmetric space group <i>P</i>2<sub>1</sub>2<sub>1</sub>2<sub>1</sub>, except for Cs<sub>2</sub>ZnGe<sub>3</sub>S<sub>8</sub>, which crystallizes in the centrosymmetric
space group <i>P</i>2<sub>1</sub>/<i>n</i>. The
structures contain chains of corner-sharing M<sup>II</sup>Q<sub>4</sub> and M<sup>IV</sup>Q<sub>4</sub> tetrahedra linked by edge-sharing
M<sup>IV</sup><sub>2</sub>Q<sub>6</sub> dimers to give a two-dimensional
structure. All phases are structurally similar to the AM<sup>III</sup>M<sup>IV</sup>Q<sub>4</sub> (A = alkali metal, Tl; M<sup>III</sup> = Al, Ga, In; M<sup>IV</sup> = Si, Ge, Sn; Q = S, Se) phases; however,
the members of this family have completely ordered M<sup>II</sup> and
M<sup>IV</sup> sites as opposed to the occupational disorder of M<sup>III</sup> and M<sup>IV</sup> over all tetrahedral sites present in
AM<sup>III</sup>M<sup>IV</sup>Q<sub>4</sub>. The structural trends
of the Cs<sub>2</sub>M<sup>II</sup>M<sup>IV</sup><sub>3</sub>Q<sub>8</sub> family are discussed, along with a systematic study of their
optical properties. Density functional theory (DFT) electronic structure
calculations were performed using the projector augmented wave method
to further investigate the trends in the band gaps of the Cs<sub>2</sub>M<sup>II</sup>M<sup>IV</sup><sub>3</sub>Se<sub>8</sub> (M<sup>II</sup> = Mg, Zn; M<sup>IV</sup> = Ge, Sn) compounds. The experimental diffuse
reflectance UV–vis spectroscopy results show that the Mg compounds
have smaller band gaps than those containing Zn for both the Ge and
the Sn families whereas the DFT calculations show the opposite trend.
Cs<sub>2</sub>HgSn<sub>3</sub>Se<sub>8</sub> was studied as a representative
example of this family using differential thermal analysis and melts
congruently at 595 °C. Crystal growth of this compound using
the Bridgman method resulted in a polycrystalline ingot from which
plate crystals ∼2 mm × 3 mm could be cleaved. The band
gap of the compounds varies from a narrow 1.07 eV for Cs<sub>2</sub>ZnGe<sub>3</sub>Te<sub>8</sub> to a wide 3.3 eV for Cs<sub>2</sub>ZnGe<sub>3</sub>S<sub>8</sub> and Cs<sub>2</sub>CdGe<sub>3</sub>S<sub>8</sub> making this family a potentially useful source of materials
for a variety of electronic applications. Cs<sub>2</sub>HgSn<sub>3</sub>Se<sub>8</sub> crystals exhibit photoconductivity response where
the photoexcited electron and hole show mobility-lifetime products
on the order of 3.69 × 10<sup>–5</sup> cm<sup>2</sup>/V
and (<i>μτ</i>)<sub>h∥</sub> = 7.78 ×
10<sup>–5</sup> cm<sup>2</sup>/V, respectively