Computational Chemistry Meets Experiments for Explaining the Geometry, Electronic Structure, and Optical Properties of Ca10V6O25

In this paper, we present a combined experimental and theoretical study to disclose, for the first time, the structural, electronic, and optical properties of Ca10V6O25 crystals. The microwave-assisted hydrothermal (MAH) method has been employed to synthesize these crystals with different morphologies, within a short reaction time at 120 °C. First-principle quantum mechanical calculations have been performed at the density functional theory level to obtain the geometry and electronic properties of Ca10V6O25 crystal in the fundamental and excited electronic states (singlet and triplet). These results, combined with the measurements of X-ray diffraction (XRD) and Rietveld refinements, confirm that the building blocks lattice of the Ca10V6O25 crystals consist of three types of distorted 6-fold coordination [CaO6] clusters: octahedral, prism and pentagonal pyramidal, and distorted tetrahedral [VO4] clusters. Theoretical and experimental results on the structure and vibrational frequencies are in agreement. Thus, it was possible to assign the Raman modes for the Ca10V6O25 superstructure, which will allow us to show the structure of the unit cell of the material, as well as the coordination of the Ca and V atoms. This also allowed us to understand the charge transfer process that happens in the singlet state (s) and the excited states, singlet (s*) and triplet (t*), generating the photoluminescence emissions of the Ca10V6O25 crystals.

For the synthesis of Ca 10 V 6 O 25 crystals, different authors reported the use of precipitation and hydrothermal methods to obtain crystals with diverse morphologies. 5,10,11 In particular, Hojamberdiev et al. 10 synthesized Ca 10 V 6 O 25 via hydrothermal processing in a basic medium under the pH range of 12.0−13.5, the temperature range of 120−180°C, and reaction times of 12, 24, and 48 h. These authors concluded that the above reaction parameters have a strong influence on the morphology of the assynthesized Ca 10 V 6 O 25 crystals, and they obtained various morphologies, such as rods and spherical, ricelike, and bundled particles. However, these methods require high temperatures, long processing times (from a few hours to a few days), and expensive equipment. However, the use of microwaves has improved the synthesis procedure since materials were obtained at shorter times and lower temperatures. Moreover, there is increased interest in developing the microwave-assisted hydrothermal (MAH) method, because it has advantages of being a faster, simpler, and more efficient route to obtain single-phase crystals with good reproducibility. 23−26 In this context, by using the MAH method, our group could synthesize various metal oxides, such as BaZrO 3 , 27 CuO with catalytic activity, 28 SrTiO 3 with photocatalytic activity, 29 and α-Ag 2 WO 4 as acetone gas sensors. 30 The present paper reports the synthesis of monophasic Ca 10 V 6 O 25 crystals by using the MAH method at a temperature of 120°C within a short synthesis time. The geometry, electronic structure, optical properties, and morphology of the crystals were examined using X-ray diffraction (XRD) patterns with Rietveld refinement, Raman spectroscopy, ultraviolet− visible (UV-vis) diffuse reflectance spectroscopy (DRS), photoluminescence (PL) measurements, transmission electron microscopy (TEM), energy-dispersive X-ray spectroscopy (EDS), field-emission scanning electron microscopy (FE-SEM), and current−voltage measurements. First-principles calculations at the density functional theory (DFT) level were performed to complement the experimental results, in order to elucidate the geometry, electronic structure, and optical properties of Ca 10 V 6 O 25 crystals. The localization and characterization of the excited singlet and triplet electronic states allows us to rationalize the PL emissions of this material, which are reported for first time in the present work. 2.2. Characterizations. Ca 10 V 6 O 25 samples were characterized by X-ray diffraction (XRD) using a diffractometer (Model DMax/ 2500PC, Rigaku, Japan), with Cu Kα radiation (λ = 1.5406 Å) in the 2θ range of 5°−75°with a scanning rate of 0.02°/min. The Rietveld refinements using the general structure analysis (GSAS) program, the scan rate of 0.01°/min for 2θ range of 5°−110°. Raman spectroscopy measurements were performed using a spectrometer (Model T64000, Horiba Jobin-Yvon, Japan) coupled to a CCD Synapse detector and an argon-ion laser, operating at 514 nm with a maximum power of 7 mW. The spectra were measured in the wavenumber range of 25−1200 cm −1 . Ultraviolet−visible (UV-vis) spectra were obtained using a spectrophotometer (Model Cary 5G, Varian, USA) in diffuse reflection mode. The morphologies of the samples were examined using fieldemission scanning electron microscopy (FE-SEM) (Supra 35-VP Carl Zeiss, Germany) operated at 15 kV. PL measurements were performed with a Monospec 27 monochromator (Thermal Jarrel Ash, USA) coupled with a R955 photomultiplier (Hamamatsu Photonics, Japan). A krypton ion laser (Coherent Innova 200 K, USA; λ = 350 nm) was used as the excitation source with an incident power of ∼14 mW on the samples. All measurements were performed at room temperature. For the Raman, PL, and UV-vis characterizations: the Ca 10 V 6 O 25 samples, in the powder form, were placed in the respective port samples of each piece of equipment.

EXPERIMENTAL
For the current−voltage (I−V) characterizations, 6-mm-diameter pressed pellets were made and the measurements were performed at room temperature, using silver electrical contacts 75 nm thick, which were obtained on an evaporator (Model AUTO 306, Edwards) under a pressure of 10 −7 mbar. The current was determined by a Keithley 6517B electrometer coupled to a probing positioning system.

COMPUTATIONAL METHODS
Calculations were performed using the periodic ab initio CRYSTAL14 package, 31 based on density functional theory (DFT) using hybrid functional of a nonlocal exchange  functional developed from Becke, combined with a correlation functional based on the gradient of electronic density developed from Lee, Yang, and Parr (B3LYP). 32,33 This computational technique has been successful for the study of the electronic and structural properties of various materials, including vanadates and several other oxides. 34−38 The Ca, V, and O atoms were described by standard atom-centered all-electron basis sets: 86-511d3G, 86-411d4G, and 6-31d1G, respectively. 39−41 Full optimization of the Ca 10 V 6 O 25 structure was performed. The initial geometry was obtained from XRD experimental results, considering the removal of one O atom in this system through the ATOMREMO option provided by the CRYSTAL program. The convergence criteria for both monoelectronic and bielectronic integrals was set as 10 −8 Hartree. Regarding the density matrix diagonalization, the reciprocal space net was described by a shrinking factor set to 4, corresponding to 12 kpoints within the irreducible part of the Brillouin zone in accordance with the Monkhorst−Pack method. 42 In order to understand the PL mechanism associated with Ca 10 V 6 O 25 material, both excited singlet states (s*) and excited triplet states (t*) have been localized and characterized, following the previous strategies developed by our group. 43−48 For the s* model, we consider an off-center V displacement of 0.1 Å in the z-direction. In this case, the t* model state was reproduced fixing the difference between spin-up (α) and spin-down (β) (nα − nβ = 2) along the self-consistent field (SCF) calculations. The electronic structure was investigated from band structure and density of states (DOS).

RESULTS AND DISCUSSION
4.1. XRD and Rietveld Refinements. Figure 1 and Figure  S1 (in the Supporting Information) present the XRD patterns and Rietveld refinement plot of the 3D Ca 10 V 6 O 25 crystals, respectively. The XRD patterns in Figure 1 show that all of the samples exhibit well-defined peaks suggesting an ordered longrange arrangement in the crystal lattice, for the samples obtained at 120°C via MAH. The Miller indices of the peaks are in accordance with Joint Committee on Powder Diffraction Standards (JCPDS) No. 52-649 for the Ca 10 V 6 O 25 phase with a hexagonal structure and the space group of P6 3 /m, indicating the absence of additional phases. Thus, the efficient internal heating by direct coupling of microwave energy with the molecules was efficient in obtaining the pure Ca 10 V 6 O 25 phase at a temperature of 120°C within short reaction times in the MAH method. The Rietveld refinement method was applied to confirm the three-dimensional (3D) structure of Ca 10 V 6 O 25 . The refinement was performed using the GSAS program. 49,50 No Inorganic Crystal Structure Database (ICSD) card related to this structure has been reported in the literature. ICSD No. 24100, for calcium tris(tetraoxochromate(V)) hydroxide, reported by Wilhelmi et al., has been used, because it has a similar crystallographic structure. 51 The obtained results are displayed in Table S1 in the Supporting Information. The experimentally observed XRD patterns and the theoretically calculated data exhibit small differences near zero on the intensity scale, as illustrated by the line Y Obs −Y Calc ; moreover, the fitting parameters (R Bragg and χ 2 ) indicate consistency between the calculated data and observed XRD patterns for the Ca 10 V 6 O 25 microcrystals obtained at 120°C. The smaller values of fitting parameters obtained for the CaVO-4 and CaVO-16 samples indicate greater network symmetry and long-range ordering than those of the powders of CaVO-8 and CaVO-32. Table S1 shows that the CaVO-4 and CaVO-16 samples present a smaller cell volume, associated with the volume contraction at the unit cell. The lattice parameters (a, b, and c) and bond angle (β) estimated from the refinement confirm the hexagonal structure. Figure 2 displays a schematic representation of a hexagonal unit cell of the Ca 10 V 6 O 25 crystal, modeled from the Rietveld refinement data and optimized with DFT/B3LYP level of theory, in which the symmetry and geometry of the local coordination of Ca and V cations forming the building blocks of this crystal are depicted.
The unit cell shown in Figure 2 was modeled using the visualization system for electronic and structural analysis (VESTA) program (version 3.4.0) for Windows 7−64-bit0. 52  2 ) and the following vibrational modes: For a perfect and orderly crystalline structure with this space and point group symmetry, six active Raman modes are expected as follows: In this study, first-principles calculations predict 123 active Raman and infrared modes for the Ca 10 V 6 O 25 structure, of which 63 Raman modes match the following decomposition at the Γ point: (Γ = 24A g ′+ 24E g ′ + 15E g ′′). The experimental vibrational Raman frequencies were obtained in the wavenumber range of 25−1200 cm −1 , and all the samples exhibited 13 experimental modes, as shown in Figure 3. However, some of them are not observed experimentally, because of either overlapping bands or low intensity.
At lower frequencies, the peaks obtained through B3LYP calculations at 89.38 cm −1 (exp 90 cm −1 ), 124.14 cm −1 (exp 126 cm −1 ), 204.69 cm −1 (exp 202 cm −1 ), 237 cm −1 (exp 235 cm −1 ), and 262.58 cm −1 (exp 276 cm −1 ) are associated with the lattice modes of [CaO 6 ] clusters. 19 The intense band at 348. As reported in the literature, 54,55 a solid with the local structural order has a sharp, intense, and well-defined vibrational bands. We have compared the full width at half-maximum (fwhm) of the peak of 352 cm −1 in the Raman spectra of all the samples ( Figure S2 in the Supporting Information). Analysis of these phonon line widths reveals similar structural disorder at the [VO 4 ] cluster. Table S2 shows the calculated B3LYP frequencies (ω) of the Raman active modes at the Γ point for the P6 3 /m structure. The results of the B3LYP calculation present an acoustic mode of zero frequency with E′ symmetry, and an imaginary frequency (−55.02 cm −1 ), which reveals that the Ca 10 V 6 O 25 structure optimized in the P6 3 /m space group has a structural instability at Γ and corresponds to a saddle point on a very flat potential energy surface after removing an oxygen atom in the initial structure. Various numerical checks (e.g., setting a better energy convergence, strengthening of the optimization criteria, decreasing the symmetry constraints) have been performed to ensure that the negative frequency was not an artifact of the calculations.
4.3. Morphology and Growth Mechanism. Variation in the synthesis time (4,8,16, and 32 min) influences the morphology of the Ca 10 V 6 O 25 crystals (see Figure 4).
The growth process can be monitored at different times, maintaining the temperature constant at 120°C. At 4 min, after the formation of the first nanoparticles, the oriented growth process of the stems occurred from the agglomerated particles. The small stems grew oriented around a single common center, forming a microparticle in the CaVO-4 sample (Figure 4a). The increase in the synthesis time to 8 min (CaVO-8 sample) favored an elongation of the stems, joined with a length of 6 μm and width of 644 nm, and their stem ends appeared faceted. Thus, the morphology is similar to a straw bundle with two fantails of stems, which are connected to each other in the middle (Figure 4b). During the synthesis, the effect of the    (Figure 4c). It can be observed that, for a synthesis time of 16 min, there was a significant reduction of isolated rods in the sample. Further increasing the synthesis time to 32 min provoked the dissolution and recrystallization processes, with a concomitant elongation of the rods ( Figure  4d). These rods were split into nanofilaments during the growth process, forming a particle with more ramifications. The CaVO-32 crystal presented tubes with the length of 6.67 μm and smaller width (230 nm) than the crystals obtained within a shorter synthesis time.
The growth process of the Ca 10 V 6 O 25 particles can be considered to be a crystal splitting mechanism. The nanocrystals are developed in large crystals, and these are divided to form stems, which are subdivided into nanofilaments as a bundle of straw shape. The division of the crystal is related to the rapid kinetics of crystal growth, supersaturation of the solution, and surface energy. 56−59 Figure 5 shows a series of morphologies formed according to the growth time of the Ca 10 V 6 O 25 particles. Thus, we observe that a single crystal is subdivided by means of a single nucleus. Along with the growth of the particle, there is a change in the [CaO 6 ] clusters, and thus, different morphologies that are dependent on the synthesis time and the presence of microwaves are observed.
It can be observed that the MAH method allowed us to obtain materials with good structural ordering at short time and low temperature (120°C at 4 min) with well-defined morphology. The interaction of the microwave energy with the particles or ions accelerates the diffusion mechanism, allowing the collision with other ions, atoms, or neighboring molecules, generating heat and thus reducing sintering time and temperature. 23 (4,8,16, and 32 min) at 120°C via the MAH method were investigated using UV-vis and PL emissions at room temperature. Ca 10 V 6 O 25 has a direct-type optical transition. 10 According to the Wood−Tauc function, 60 αhν = C 1 (hν − E gap ) n , where n = 1 / 2 , α is the absorption coefficient, hν is the photon energy, C 1 is a proportionality constant, and n is the type of electronic transition. Thus, we have (αhν) 2 , which can be related to the Kubelka−Munk function (K−M), 61  These interactions produce localized electronic levels within the forbidden band gap, which cause the entrapment of electrons and holes. Thus, the intrinsic PL emissions can be associated with these mechanisms, which are derived from the interactions between distorted clusters. In this way, the coupling of the vibrational and rotational movements modifying the intrinsic properties generating new materials. These properties are related to the defect densities, that is, order−disorder of the crystals.
To clarify the electronic structure of Ca 10 V 6 O 25 , total and atom-resolved density of states (DOS) and band structures profiles were obtained, and the corresponding results are presented in Figure 6. In the left panel (Figure 6a), the band structure profile for Ca 10 V 6 O 25 is presented, in the middle panel (Figure 6b), the total and atom-resolved DOS curves are presented, whereas in the right panel (Figure 6c), a clusterresolved DOS curve is depicted focusing on the contribution of   6 ] clusters with singular symmetries. An analysis of the both valence and conduction bands (VB and CB, respectively) show a pattern, which is directly associated with the local clusters centered on Ca and V cations. The VB was predominantly composed of the orbitals of oxygen anions with a small content of Ca orbitals. In contrast, the CB was mostly based on empty valence orbitals from V cations hybridized with oxygen atomic orbitals, revealing the role of [VO 4 ] clusters.
Let us now briefly discuss the relationship between the local coordination of both V and Ca cations and the electronic structure of the Ca 10 V 6 O 25 crystal. The optimized crystalline structure obtained for Ca 10 V 6 O 25 indicates that Ca cations have a 6-fold coordination [CaO 6 ] with distinct local environments, as presented in Figure 2. Despite the same coordination number, the local arrangement indicates the formation of distorted octahedral, prism, and pentagonal-pyramidal symmetries. These distorted polyhedral symmetries provoke a local disorder along the crystalline structure, which perturbs the energy level distribution in the VB. From the energy levels distribution depicted in Figure 6c, it can be observed that the VB region exhibits two intermediate levels of energy, which can be directly related to the local geometries associated with Ca-centered clusters. Indeed, the first contribution located between −3.15 eV and −2.28 eV is related to the presence of all Ca-centered clusters with a major contribution of approximately prismatic [CaO 6 ] clusters. In addition, it was noted that, at the vicinity of the Fermi level (between −0.46 eV and 0.0 eV), the electronic states are related to the distorted Ca-centered octahedral clusters. Therefore, the distortion associated with the crystalline structure of the Ca 10 V 6 O 25 results in a singular energy-level distribution that controls its electronic properties.
In addition, the obtained band structure profiles indicate that both VB maxima and CB minimum regions present flat energy bands against the symmetry points, resulting in a small difference between the direct and indirect band gap values, which helps achieve superior electrical and optical properties. The calculated band gap is 3.35 eV; in contrast, the experimental value reported here is 4.04 eV. This difference can be associated with almost two factors, as follows: (i) the as-synthesized Ca 10 V 6 O 25 materials exhibits a high degree of structural disorders with the presence of intermediary energy levels at the forbidden region, and (ii) the theoretical values are computed by using the hybrid B3LYP functional and their drawbacks to obtain accurate values of the band gap are wellknown. 62, 63 Hojamberdiev and co-workers 10 successfully used hydrothermal methods to grow Ca 10 V 6 O 25 crystals, which showed a semiconducting behavior with band-gap values of ∼3.7 eV, which is consistent with our theoretical and experimental data. In this case, it can be assumed that the electron transfer associated with the band-gap value involves the excitation of VBM electrons, which are located at the orbitals linked to the Ca−O bonds of the highly distorted octahedral [CaO 6 ] clusters, to orbitals or empty states located at the V−O bond of the [VO 4 ] clusters. Figure 7 shows the PL spectra at room temperature, with the wavelength of excitation of 350 nm. All of the samples had a broadband profile covering the entire visible region of light. The PL spectra were deconvoluted to understand the behavior of the PL property of the Ca 10 V 6 O 25 samples. The Voigt Area G/L function was used, and three components were centered in the yellow (2.12 eV, 585 nm), green (2.43 eV, 510 nm) and blue (2.79 eV, 444 nm) regions.

PL Emissions.
It can be observed that the CaVO-4 and CaVO-16 samples have a higher percentage of emission in the blue and green regions, whereas, for the CaVO-8 and CaVO-32 samples, a higher percentage of emission in the yellow region is observed, which is related to the presence of the intrinsic structural defects of the samples. These defects generate intermediated levels between VB and CB. Therefore, the fast growth process and formation of smaller stems causes a high concentration of defects associated with structural distortions in the [VO 4 ] clusters. An analysis of the deconvolution of PL emissions displayed in Figure 7a renders that emission energy in the yellow region corresponds to 2.12 eV, being lower than the energies in  Figure  7b).
Both dissolution and recrystallization processes during the synthesis favor the formation of elongated stems in these samples, generating oxygen vacancies and surface defects. Three different charge states of oxygen vacancies may occur: the [VO 3 .V 0 x ] state, which presents two paired electrons and is neutral in relation to the lattice; the singly ionized [VO 3 .V 0 . ] state, which has one unpaired electron; the [VO 3 .V 0 ·· ] state, which is doubly positively charged, with respect to the lattice. It is believed that these different types of structural defects that are generated by medium-range distortion that give rise to PL at room temperature. Since, the distortion causes the polarization in the structure and enable the formation of localized states in the band gap, as well as the inhomogeneous charge distribution in the cell, allowing the entrapment of electrons. The distribution of the localized levels allows various energies to be able to excite the trapped electrons. Broadband PL emission for all Ca 10 V 6 O 25 samples (Figure 7) shows the participation of numerous energy levels within the band gap, where the shift observed in the maximum emission point is due to variations on the density of structural defects.
A PL mechanism for disordered solids has been very reported in the literature and first-principles calculations are very important to elucidate such a mechanism. 46,47,64 In such mechanism structural defects, the creation of oxygen vacancies from the disorder of clusters, as the building block of the material is responsible for the formation of excited singlet (s*) and triplet (t*) electronic states related to PL phenomena. In particular, for our Ca 10 V 6 O 25 samples synthesized at various times, the experimental results show a similar response; thus, structural defects are important to investigate this material. Oxygen vacancies are the strongest evidence of the structural and electronic disorder in [CaO 6 ] clusters; high concentration of disorder in clusters results in excited electronic states. Therefore, we proceed to the localization and characterization of the excited electronic states of the Ca 10 V 6 O 25 system. 4.4.2.1. Excited States. Figure S4 in the Supporting Information, shows the 3D optimized structure of the excited states, singlet (s*) and triplet (t*), and the local structures of the constituent clusters, which are compared with the fundamental structure of the fundamental singlet electronic state (see Figure  2). First, we note that the obtained geometries for s* and t* exhibit imaginary frequencies (see Table S3 in the Supporting Information). The singlet excited electronic state, s*, as the ground state (Table S2) corresponds to a saddle point (−79.33 cm −1 ) on a very flat potential energy surface, whereas the excited triplet electronic state, t*, exhibits a very high and negative imaginary frequency (−1966.99 cm −1 ), showing large structural instability. All attempts to adjust the geometries and eliminate these negative values were unsuccessful.
An analysis of Figure S4 shows that three different local arrangements with singular symmetries (D 3h , C 5v , and O h ) were observed for both s* and t*. The DOS and band structure profiles obtained for the fundamental and excited states are depicted in Figure S5 in the Supporting Information. Regarding the calculated band-gap value for s*, a similar value (3.29 eV) to the electronic ground-state was observed, as the VB is mainly composed of O (2p) states and the CB is predominantly formed by the V (3d) atomic state ( Figure S5a in the Supporting Information). The main differences were attributed to the band degeneration in the s* state (Figure S5a), which can be attributed to the displacement of V atoms in the [VO 4 ] cluster.
In addition, the calculated band structure for the t* state ( Figure  S5b) indicates a band-gap value of 1.35 eV, which is a reduced value, in comparison with the singlet ground state. This electron transfer mechanism was described as a charge transfer from the 2p orbitals of disordered octahedral [CaO 6 ] clusters to the 3d orbitals of [VO 4 ] clusters ( Figure S5b), indicating that the unpaired electron density generated in the t* state is located in the 3d empty orbitals of V atoms. The electron transfer from VB to CB perturbs the electron density distribution along the [CaO 6 ] clusters, reordering the charge in the crystalline structure once the uppermost contributions of VB related to the presence of distorted octahedral clusters become high in energy, relative to the molecular orbitals of prismatic and pyramidal clusters.
Therefore, this wideband model enables the observation of the electronic features associated with the transformation from a fundamental s state to excited s* and t* states. In the CB, the t* state induces the creation of intermediary energy levels near the band-gap region responsible for the trapping of excited electrons. The calculated results confirm the electron transfer mechanism predicted from the DOS and band structure profiles ( Figure 6). Notably, the unpaired density is mainly located on the [VO 4 ] clusters closer to the highly distorted [CaO 6 ] octahedra. The high distortion of [CaO 6 ] clusters causes an increase in VBM, featuring the electronic excitation process as a charge transfer from [CaO 6 ] clusters to [VO 4 ] clusters. Therefore, the PL process is understood in the first moment as an excitation from the fundamental state (s) to an excited energy state (t*), which possesses a relative energy of 3.41 eV, in comparison with the ground state. The subsequent step can be described as an intersystem crossing process from the excited t* state to an s* electronic state, which exhibits a lower relative energy (1.03 eV), compared with the fundamental state. Once this excited s* electronic state is sufficiently populated, the PL emission occurs with a concomitant return to a ground electronic state.
The transformations from fundamental s ( Figure 2) to both excited s* and t* electronic states ( Figure S4), at prismatic (D 3h ) and pyramidal (C 5v ) clusters, are accompanied by a local disorder for both short and long Ca−O bonds, showing a general shortening of the chemical bonds. In contrast, the octahedral (O h : centered in Ca5−7) cluster shows a bond expansion from the fundamental s state to the excited s* state, whereas the transformation from s* to t* is accompanied by a bond contraction. Regarding the structural disorders associated with the tetrahedral [VO 4 ] cluster, it was observed that the transformation from s to s* involves the off-center displacement of V atoms in the z-direction, resulting in an in-plane bond elongation and out-of-plane bond contraction. This local disorder also affects the other V atoms in the crystalline structure exhibiting distorted V−O bonds. Furthermore, the transformation from s* to t* suggests a higher local disorder for [VO 4 ] clusters, where the V−O bond length increases.
A careful inspection of the obtained values indicates that the transformation from the fundamental s state to the excited s* and t* states is predominantly attributed to the symmetrical stretching vibration of the V−O bond associated with the mode described by four degenerated frequencies: 859.60 cm −1 in the fundamental state and 854.88 cm −1 in the s* state, which becomes nondegenerated for the t* state, which exhibits frequencies of 531.25 and 830.70 cm −1 , consistent with the structural disorders summarized in Figure S4. This suggests a transition to a lower symmetry without bond breaking, which

Inorganic Chemistry
Article involves the structural order−disorder effect originating from the off-centering V displacement, modifying not only the V−O bond lengths, but also the interaction among the electronic distributions of the atoms of the cell.
4.5. Measurements of Current versus Voltage. Figure 8 shows the current−voltage (I−V) characterization of the Ca 10 V 6 O 25 samples. The curves showed that the electric current in the samples presented a linear dependence with the voltage, showing an ohmic character at room temperature. It can be observed that the CaVO-4 and CaVO-32 samples showed lower electrical conductivity, compared with the CaVO-8 sample. This is possibly due to the trapping of electrons, which would be free to conduct; one reason for this behavior is the presence of oxygen molecules adsorbed on the surface or to the electron− hole recombination process. The CaVO-8 sample exhibited a greater conductivity than the other samples, and thus, it has a greater availability of free electrons. The CaVO-8 sample has numerous vanadium−oxygen vacancy centers, because of a higher percentage of emission in the yellow and red regions (see Figure 7). Oxygen vacancies form positive charges in the Ca 10 V 6 O 25 crystal lattice, favoring the diffusion of electrons when an external voltage is applied. Thus, a large current was observed in the CaVO-8 sample. However, for the CaVO-16 sample, a very high resistance was observed and the conductivity was not measured ( Figure S6 in the Supporting Information). From the PL spectrum, it was observed that this sample has a higher emission in the blue and green regions, which are directly related to the intrinsic structural defects. These defects trap electrons, increasing the resistivity of the material. Moreover, in this sample, the interconversion of octahedral clusters to prismatic and pyramidal clusters of calcium may have occurred. These prismatic and pyramidal clusters show a tendency to form materials with resistivity character. In addition, the morphology of the CaVO-16 sample may have favored these more-resistive calcium clusters.
From the theoretical point of view, the electrical properties of the Ca 10 V 6 O 25 crystal can be understood using the symmetryadapted molecular orbitals depicted in Figure 6, where the VB is described by two different oxygen contributions, because of the existence of several [CaO 6 ] clusters. Therefore, the existence of conductive behavior of the samples can be attributed to the presence of highly distorted octahedral clusters contributing to the upper part of VB, whereas the resistive response is related to the pyramidal and prismatic clusters that contribute to the inner VB region.
However, all the samples exhibited low conduction, which is a characteristic of semiconductor materials. It can be observed that the synthesis time influenced the ordering of the material and the transport properties of electrons.

CONCLUSIONS
A facile, fast, and environmentally friendly method was reported for the synthesis of Ca 10 V 6 O 25 crystals. This new structure was prepared via the MAH method, which favors the growth of crystals with different morphologies through time variation. The XRD and Raman patterns showed a complex structure with P6 3 / m space group symmetry, formed by distorted [VO 4 ] with various distorted [CaO 6 ] clusters. Well-faceted and highly crystalline microcrystals were observed, consistent with the XRD and theoretical and experimental Raman spectroscopic analysis. The degree of short organization of the Ca clusters is a determinant of PL emissions. The charge transfer process between [VO 4 ] and [CaO 6 ] clusters is responsible for the presence of the singlet and triplet excited electronic states. In addition, the strong influence of defects (intrinsic structural defects and oxygen vacancy) on the electron diffusion in the samples can be observed. The sample that exhibited a greater percentage of oxygen vacancies favored the electron transport. Furthermore, depending on the synthesis conditions used for obtaining these crystals, different morphologies and distortions in their lattice, mainly associated with the distortions of the [VO 4 ] and [CaO 6 ] clusters, can be observed, and thus, they can exhibit different electronic properties. These results summarize the relevant contributions to the understanding of the structural, electronic, and optical properties of Ca 10 V 6 O 25 crystals and the growth mechanism involved during the MAH processing.

* S Supporting Information
The Supporting Information is available free of charge on the ACS Publications website at DOI: 10.1021/acs.inorgchem.8b02807.
Rietveld refinements and DFT calculations for Ca 10 V 6 O 25 material; Raman frequencies and calculated B3LYP frequencies (ω) of the Raman active modes at the Γ point for the P6 3 /m structure; Raman frequencies calculated for Ca 10 V 5 O 25 crystal in the singlet (s*) and triplet (t*) excited state; full width at half-maximum of the peak of 352 cm −1 in the Raman spectra of all the Ca 10 V 5 O 25 samples; UV-vis diffuse reflectance spectra for Ca 10 V 6 O 25 samples; schematic representation of the constituent clusters; total and atom-resolved DOS and bands structures profiles at s* and t* electronic states; current−voltage characterizations for the Ca 10 V 6 O 25 crystal at 16 min in 120°C by MAH at room temperature (DOC)

Accession Codes
CCDC 1851953−1851956 contain the supplementary crystallographic data for this paper. These data can be obtained free of charge via www.ccdc.cam.ac.uk/data_request/cif, or by emailing data_request@ccdc.cam.ac.uk, or by contacting The Cambridge Crystallographic Data Centre, 12 Union Road, Cambridge CB2 1EZ, UK; fax: +44 1223 336033.

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