Continuously controllable optical band gap in orthorhombic ferroelectric KNbO3-BiFeO3 ceramics by

The optical bandgap of orthorhombic ferroelectric KNbO 3 is shown to be continuously controllable via Bi and Fe co-substitution according to a K 1-x Bi x Nb 1-x Fe x O 3 doping mechanism. The room temperature X-ray diffraction data combined with Raman spectroscopy analysis show the polar orthorhombic crystal structure to persist up to x ¼ 0.25, while the bandgap narrows monotonically by 1 eV ( (cid:2) 33%). In-situ Raman spectroscopy corroborates the polar nature of all compositions in the temperature range of –100 to 200 (cid:3) C. The ability to control the bandgap while maintaining the spontaneous polarisation makes the K 1-x Bi x Nb 1-x Fe x O 3 system interesting for photoinduced processes in a wide temperature range. V C 2017 Author(s). All article content, except where otherwise noted, is licensed Creative Coupling of light absorption in ferroelectrics (FEs) with properties such as photovoltage, 1 photostriction, 2 photoelas-ticity 3 and photocatalysis

The optical bandgap of orthorhombic ferroelectric KNbO 3 is shown to be continuously controllable via Bi and Fe co-substitution according to a K 1-x Bi x Nb 1-x Fe x O 3 doping mechanism. The room temperature X-ray diffraction data combined with Raman spectroscopy analysis show the polar orthorhombic crystal structure to persist up to x ¼ 0.25, while the bandgap narrows monotonically by 1 eV ($33%). In-situ Raman spectroscopy corroborates the polar nature of all compositions in the temperature range of -100 to 200 C. The ability to control the bandgap while maintaining the spontaneous polarisation makes the K 1-x Bi x Nb 1-x Fe x O 3 system interesting for photoinduced processes in a wide temperature range. Coupling of light absorption in ferroelectrics (FEs) with properties such as photovoltage, 1 photostriction, 2 photoelasticity 3 and photocatalysis 4 can be exploited to create novel photoactive devices. Interestingly, the photoresponse of FEs is characterised by photovoltages that exceed several times their bandgap values. 1,5 Moreover, the internal electrical field arising from the spontaneous polarization exhibited by FEs may be employed to separate photogenerated charge carriers, enabling them to reach the surface and subsequently to interact and react with molecules in the surrounding media. In principle, photo-induced currents can also be established, provided that bandgaps of FEs are able to capture a vast range of the solar spectrum. BiFeO 3 with a band gap of $2.67 eV has long been recognized to have the narrowest bandgap among robust ferroelectric perovskite oxides, while most ferroelectrics have bandgaps wider than 3 eV. These wide bandgaps limit light absorption primarily to the ultraviolet region; therefore, these materials are only able to capture $8-20% of the solar spectrum. 6  Bandgap engineering of FEs into the visible is emerging as an active research area. It has been shown that chemical doping can be strategically employed to successfully narrow the bandgap of KNbO 3 (KN), a well-known ferroelectric. 6,9,10 In the classic work by Shirane et al., 11 the room-temperature spontaneous polarisation of single-domain KN was reported as 41 6 2 lC/cm 2 . This large spontaneous polarisation was rationalised on the basis of the non-centrosymmetric position of Nb 5þ cations within the NbO 6 octahedra. This distortion is driven by the hybridisation of the empty d-orbitals of Nb 5þ with the O 2À p-orbitals. The relative wide optical bandgap of pure KN is also linked to the nature of the bonding between O anions and Nb cations. The large differences in electronegativity between the O and the Nb ions leads to the valence band to be formed by the 2p O states and the conduction band by the d states of the Nb transition metals sitting within the O octahedra. Hence, the excitation across the band gap in KN is essentially a charge transfer from the O 2p states at the valence band maximum (VBM) to the Nb d states at the conduction band minimum (CBM). 12 One of the strategies to narrow the band gap is by shifting up the VBM. In terms of doping, this may be achieved through substitution of Nb 5þ in KN by lower valence Me 3þ dopants. The repulsion between non-bonding 3d n orbitals of Me 3þ and 2p 6 orbitals of O 2may lead to a higher VBM.
Grinberg et al. 6 showed the bandgap of ferroelectric (1-x)KNbO 3 -xBaNi 0.5 Nb 0.5 O 3-d (KBNNO) ceramics to be tailored to values as low as 1.39 eV for x ¼ 0.10. Nevertheless, in this system, the presence of oxygen vacancies may contribute to $0.5 eV of the total band gap narrowing. Moreover, oxygen vacancies are detrimental to polarization switching and may also trap photogenerated charge carriers. Yu et al. In this letter, the crystal structure and band structure of (1-x)KNbO 3 -xBiFeO 3 (KNBF) (0 x 0.25) were investigated by X-ray powder diffraction combined with Raman spectroscopy and diffuse reflectance ultraviolet and visible spectroscopy (DRUV-vis). Previously, 9 it was shown that the bandgap of KN can be modified by dopants other than transition metals, here the ability to systematically control the bandgap of KNbO 3 by varying the content of BiFeO 3 is shown. The simultaneous replacement of K þ and Nb 5þ by Bi 3þ and Fe 3þ , respectively, is expected to prevent the formation of lattice defects, such as oxygen vacancies. Nevertheless, this premise is still to be experimentally proved in future investigations, because the photovoltaic effect induced by the electromigration of oxygen vacancies is unstable. 13 The Fe 3þ substitution for higher-valence Nb 5þ may give rise to increased repulsion between the O 2p and Fe 3d states and thereby to a higher VBM.
KNBF ceramics were fabricated as described elsewhere 9 using the following precursor powders, K 2 CO 3 (>99.0% Sigma-Aldrich), Nb 2 O 5 (>99.9%, Sigma-Aldrich), Bi 2 O 3 (>99.9%, Sigma-Aldrich), and Fe 2 O 3 (>99.9%, Sigma-Aldrich). XRD patterns were acquired using a PANalytical diffractometer (model Empyrean) in the 2h range 20-80, with a step size of 0.02 , and with a scan length of 600 s per step. Raman spectra were obtained with a Renishaw Raman microscope (model InVia) using a 532 nm solid state (100 mW) laser, in back-scattering geometry. Temperature-dependent Raman measurements were carried out using a Linkam stage (model THMS600). Capacitance measurements were carried out with an Agilent LCR meter (model e4980A). Finally, DRUV-vis spectra were acquired in the range 200-1600 nm using a Shimadzu UV-VIS-NIR Spectrophotometer (model UV-3600 Plus). Fine BaSO 4 powder was used as a nonabsorbing standard. To estimate the band gaps, first the Kubelka-Munk (K-M) function given below was calculated where R is the experimental reflectance referred to the BaSO 4 standard. Hereafter, the K-M function (or F(R) curves) is considered to be proportional to the optical absorption. Hence, the absorption coefficient, a, can substituted by F(R) in the Tauc equation where h is the Planck's constant, is the frequency of vibration, a is the absorption coefficient, E g is the bandgap, and A is the proportional constant; for direct allowed transition, n ¼ 2 and for indirect allowed transition, n ¼ 1/2. Fig. 1 shows the room-temperature XRD data for KNBF ceramics. Within the detection limits of the technique, all ceramics appear to be single-phase, as shown in Fig. 1(a). All reflections in the XRD data for undoped KN can be assigned to an orthorhombic perovskite described by the Amm2 space group. The typical peak splitting expected for a perovskite with orthorhombic crystal symmetry is clearly evident in undoped KN, but within the resolution of our measurements, only single peaks are visible for doped ceramics, as shown in Fig. 1(b); however, Raman spectroscopy provides a strong evidence that these materials are isostructural. Reflections shift slightly but systematically towards higher 2h angles with increasing x, indicating that the co-solubility of BiFeO 3 and KNbO 3 is accompanied by a decreasing unit cell volume. The average orthorhombic crystal symmetry for the doped compositions is also corroborated by the Raman spectroscopy data shown in Fig. 2. The typical spectral features exhibited by the ferroelectric KNbO 3 orthorhombic polymorph are also visible in the Raman spectra of all doped ceramics. This spectral similarity is sufficient to simultaneously ascertain the orthorhombic crystal symmetry and the occurrence of longrange polar order in the doped materials as explained below.
From the group theory analysis, orthorhombic KN (x ¼ 0) should exhibit 12 Raman active optical modes of 4A 1 þ 4B 1 þ 3B 2 þ A 2 symmetries, which can be separated into translational modes of isolated K þ and internal modes of the NbO 6 octahedra. Modes in the KN Raman spectrum are labelled according to the single-crystal assignment by Quittet et al. 14 Hence, in the low-to mid-wavenumber region, the Raman spectrum of KN is characterised by (i) a mixed sharp mode at 192 cm À1 , (ii) a Fano-type interference dip at 197 cm À1 , (iii) a broad B 1 (TO) mode centered at 250 cm À1 , (iv) a B 1 (TO) at 272 cm À1 , (v) a sharp mode at 278 cm À1 , (vi) and another mode at 294 cm À1 . Spectral features (i), (ii), and (vi) are believed to be a fingerprint for the occurrence of long-range polar order in KNbO 3 . The sharp mode at 192 cm À1 is actually a mixed mode due to B 1 (TO), A 1 (TO), A 1 (LO), and B 2 (TO) modes, while the mode at 294 cm À1 is due to A 1 (LO) and A 1 (TO), but because of the resolution limit of the instrument, they appeared merged as a single peak. The high wavenumber region (>500 cm À1 ) of the Raman spectrum of KNbO 3 is characterized by a (vii) a B 1 (TO) mode at $532 cm À1 , (viii) a A 1 (TO) mode at $600 cm À1 , (ix) a low intensity A 1 (LO) mode at 831 cm À1 .
Upon doping, new modes emerge in the low frequency regime; however, since at this stage, information on their origin is merely speculative, they are merely labelled as 1 and 2. The new mode 1 is relatively broad and appears $110 cm À1 , whereas mode 2 appears as a shoulder to the sharp mixed mode at 192 cm À1 . The relative intensity of mode 2 appears to increase with increasing x. In the past, these modes have been associated with A-O vibrations, in particular, to nmsized clusters rich in either Bi 3þ or K þ cations. 15 Finally, the A 1 (LO) mode at 831 cm À1 appears to become broader with increasing x. This broadening may be associated with the emergence of new modes too, as previously observed, due to breathing of the octahedra, when occupied by different B cations. 9 The general broadening of the Raman modes from the doped ceramics, Fig. 2, results from increased lattice disorder, which manifests itself by the emergence of Urbach tails in the Tauc plots (Fig. 5).
Polarization, P, vs electric field, E, measurements (as will be shown elsewhere) gave unsaturated PE loops, with the exception for KN, which was considered an inconclusive response for unambiguously determining ferroelectricity. Raman spectroscopy, however, is a more reliable technique to determine the non-centrosymmetric polar character of the samples, as previously shown. 9,15 The presence of a sharp mode at 192 cm À1 is sufficient to prove the occurrence of long-range polar order in all compositions studied, as shown in Fig. 2(b). In a previous work, 15 monitoring of this mode was employed to show the replacement of long-range polar order by short-range polar order in (1-x)KNbO 3 -xBiYbO 3 ceramics for x ¼ 0.20 and 0.30. These two compositions exhibit so-called weak relaxor behaviour, 15 which may be regarded as a re-entrant dipole glass behaviour. 16 The temperature dependence of the relative permittivity for KNBF (x ¼ 0, 0.05, and 0.25) ceramics measured at 100 kHz is illustrated in Fig. 3. KN shows two clear dielectric anomalies at 394 C and 206 C, which can ascribed to the cubic-to-tetragonal and to the tetragonal-to-orthorhombic structural phase transitions. On the single-crystal, these transitions were reported to occur on heating at 420 C and 220 C, respectively. 11 This temperature discrepancy may be ascribed to the impurities present in the starting raw materials, in particular, in K 2 CO 3 , which has the lowest purity. Although these anomalies are also present in all doped samples, their magnitude is decreased. x ¼ 0.25 ceramics show the highest apparent relative permittivity over the entire temperature range considered, but this may be a consequence of the fact that they have the lowest bandgap, as discussed later.
In-situ Raman spectroscopy analyses were carried out in the -100 to 200 C temperature range in order to assert the presence of long-range polar order over a wide temperature range. For the sake of simplicity, data are only presented for KN, x ¼ 0.05 and 0.20 at three different temperatures (-100 C, 25 C, and 200 C). In Fig. 4(a), the spectra collected at -100 C show, in the 150-300 cm À1 region, the spectral signature typical for the ferroelectric rhombohedral polymorph. On heating to 25 C, the low frequency region becomes consistent with the ferroelectric orthorhombic polymorph, as shown in Fig. 4(b). Finally, at 200 C, close to the dielectric anomalies in Fig. 3, splitting between B 1 (TO) and A 1 (TO) modes in the medium frequency range becomes less evident as x increases, all compositions, however, still show the features of long-range polar order. It is also worth noting that the aforementioned modes 1 and 2 are present at all temperatures. Hence, based on both permittivity measurements and Raman spectroscopy analysis, all ceramics studied exhibit dielectric anomalies associated with structural phase transitions, and their ferroelectric nature is corroborated by the presence of a Fano-type resonant dip in their Raman spectra. 9, 15 We conclude, therefore, that all studied ceramics are ferroelectric in a wide temperature range.
Finally, diffuse reflectance spectroscopy was carried out using photons with wavelengths ranging from 200 to 1600 nm. The bandgaps of KNBF ceramics were determined using the Tauc plots in Fig. 5. The bandgap energies were obtained from the intercept of the tangent line in the plot of hF R ð Þ ½ n vs energy. Currently, there is no information about whether the band gap of KNBF is direct or indirect. Hence, in Fig. 5(a), the Tauc plot is constructed for n ¼ 2 (direct bandgap). The value extracted for KN is 3.66 eV, a high value but within the range reported in the literature, 6 and consistent with the fact that these ceramics were able to withstand an applied electric field of 80 kV/cm. For x ¼ 0.05, the value drops to $3.22 eV; however, this still high value is inconsistent with the inability of these ceramics to withstand an electrical field as low as 5 kV/cm. Indeed, all KNBF ceramics were electrically very leaky, suggesting band gaps remarkably lower than 3 eV. Hence, in Fig. 5(b), the Tauc plot is constructed using n ¼ 1/2 (indirect bandgap). The extracted bandgaps for KN and x ¼ 0.05 are $3.22 eV and $2.5 eV, respectively, consistent with their electrical resistances. With increasing x, the bandgap narrows continuously, reaching $2.25 eV for x ¼ 0.25. We note that the apparent increase in the relative permittivity, Fig. 3, appears to follow the narrowing of the bandgaps, Fig. 5. A correlation between the dielectric response and optical behaviour of several other KNbO 3 -based solid solutions is reported elsewhere. 6,17 The Tauc plot in Fig. 5(b) is marked by photoresponsive phenomena other than the direct charge transfer between O and Nb atoms, i.e., across the bandgap. Around 2.5 eV, there is a clear shoulder, present in all doped materials, whose magnitude increases with increasing x. The optical absorption spectra of Fe 3þ containing substances are known to exhibit three types of electronic transitions, namely, Fe 3þ ligand field transitions or the d-d transitions, ligand to metal charge transfer transitions, and pair excitations resulting from the simultaneous excitation of two neighbouring Fe 3þ that are magnetically coupled. Bukert et al. 18 carried out an optical spectroscopy study in BiFeO 3 and observed three well-defined absorption features at 1.22 eV, 1.66 eV, and 2.14 eV, which were assigned to charge-transfer excitons and in-gap defect states probably related to oxygen vacancies. More experiments are underway to gather a further insight into the phenomena observed in Fig. 5(b). All KNBF show Urbach tails; however, their appearance in optical absorption near band edges are expected in any material with disorder having a correlation length of order of the interatomic spacing, as this causes fluctuations in the electron energies $(eV) 2 .
Crystal chemistry arguments can be recalled to partially explain bandgap narrowing in KNBF as follows: (i) the replacement of Nb 5þ by Fe 3þ creates underbonded O 2adjacent to the Fe 3þ , which form FeO 6 octahedra, (ii) Bi 3þ which tend to be off-center, create short, strong Bi-O (covalent) bonds that partially compensate for the loss of B-O bonding, (iii) K þ do not off-center and are less prone to compensate the decrease B-O bonding. As a result, the repulsion between the non-bonding O charge densities and Fe 3d states is relatively weak, leading to an upshift of the VBM, which is composed of O 2p and Fe 3d states. The lattice distortion decreases markedly with x increasing from 0 to 0.05 and remains small (i.e., below the resolution limit of X-ray diffraction) above this concentration, as shown in Fig. 1. Coincidentally, the bandgap narrowing is the greatest in this compositional range as shown in Fig. 5, and the A 1 (LO) and A 1 (TO) modes exhibit the largest shift, as shown by the dashed lines in Fig. 2. Hence, the magnitude of distortion is expected to have a major effect on the bandgap, modifying both CBM and VBM. The exact effect will depend on the coupling between the lattice strain and atomic displacements, understanding of which obviously requires further studies.
In summary, it was demonstrated that the band gap of orthorhombic ferroelectric KNbO 3 can be systematically narrowed by 1 eV (i.e., a $33% reduction) via co-substitution of K and Nb by Bi and Fe, respectively. Remarkably, this bandgap narrowing is achieved while maintaining long-range polar order over a wide temperature range. C.P.G. acknowledges SHU for a VC doctoral scholarship. Ian M. Reaney acknowledges the support from the Engineering and Physical Sciences Research Council through EP/L017563/1.