On the incorporation of nickel into hexagonal barium titanate: magnetic properties and electron paramagnetic resonance (EPR)

Systematic measurements of the magnetic moment of hexagonal 6H-BaTiO3 + 0.04 BaO + x NiO (0.005 ≤ x ≤ 0.02) ceramics were performed to study the influence of Ni ions on the magnetic properties. By temperature-dependent measurements of the paramagnetic susceptibility at 90 kOe, the Ni2+ ion was identified as the majority defect in air-sintered Ni-doped hexagonal barium titanate. Q-band EPR investigations of a 2.0 mol% Ni-doped single crystal revealed three different Ni centers located at Ti sites: first, Ni3+ ions at Ti sites in intact oxygen octahedra, second, Ni3+ associated with an oxygen vacancy and third, the presence of Ni2+ centers leading to a forbidden transition. The Ni3+—VO associate characterized by a vacancy in the face-sharing oxygen plane of the oxygen octahedra can be ruled out. The crystal field parameters of the Ni2+ defect were estimated by a combined fitting of the paramagnetic susceptibility and the EPR fine structure parameter D to B04\documentclass[12pt]{minimal} \usepackage{amsmath} \usepackage{wasysym} \usepackage{amsfonts} \usepackage{amssymb} \usepackage{amsbsy} \usepackage{mathrsfs} \usepackage{upgreek} \setlength{\oddsidemargin}{-69pt} \begin{document}$$B_{0}^{4}$$\end{document} ≈ −17,300 cm−1, B02\documentclass[12pt]{minimal} \usepackage{amsmath} \usepackage{wasysym} \usepackage{amsfonts} \usepackage{amssymb} \usepackage{amsbsy} \usepackage{mathrsfs} \usepackage{upgreek} \setlength{\oddsidemargin}{-69pt} \begin{document}$$\left| {B_{0}^{2} } \right|$$\end{document} ≈ 2500 cm−1 and B34\documentclass[12pt]{minimal} \usepackage{amsmath} \usepackage{wasysym} \usepackage{amsfonts} \usepackage{amssymb} \usepackage{amsbsy} \usepackage{mathrsfs} \usepackage{upgreek} \setlength{\oddsidemargin}{-69pt} \begin{document}$$B_{3}^{4}$$\end{document} ≈ 19,000 cm−1.


Introduction
Barium titanate as the prototype of the large perovskite oxide family with ferroelectric and piezoelectric properties is in the focus of solid-state research since decades. Aside from the continuous materials' investigation for capacitors, actuators and other passive electronic components, its potential multiferroic properties and the fact that suitably doped BaTiO 3 is a dilute magnetic oxide (DMO) [1][2][3][4] proves the importance of further research on this material. DMOs or oxide diluted magnetic semiconductors (O-DMS) are promising materials for spintronics and magneto-optics [4][5][6]. While most of the related investigations used iron as dopant [1][2][3][4][7][8][9], previously also nickel-doped BaTiO 3 was studied [9][10][11].
Barium titanate (BaTiO 3 ) has a variety of phase transitions. Besides the well-known temperaturedriven phase transitions cubic À! 125 C tetragonal À! 0 C orthorhombic À! À90 C rhombohedral of the modifications with 3C stacking, this perovskite possesses a hexagonal high-temperature phase with 6H stacking, which can be stabilized down to room temperature via sintering and cooling in reducing atmosphere [12] or by doping with several 3d transition elements [13][14][15]. The 6H modification of BaTiO 3 exhibits its own series of temperature-driven phase transitions [16,17]: The hexagonal 6H polytype of BaTiO 3 (space group P6 3 /mmc) has two non-equivalent Ti sites per unit cell with trigonal symmetry. The Ti(1) site refers to the 2a position (0, 0, 0) belonging to exclusively corner-sharing oxygen octahedra, while Ti(2) refers to the 4f position (1/3, 2/3, 0.154) belonging to a Ti 2 O 9 unit of two face-sharing oxygen octahedra. In the following, the face-sharing oxygen ions are denoted as O(1) and the ones connecting the Ti 2 O 9 units and the corner-sharing octahedra as O (2). This labeling of the atoms follows the one of Burbank and Evans [18]. The unit cell of hexagonal 6H-BaTiO 3 can also be described by six BaO 3 layers (i.e., [Ba(2)O(2) 3-Ba(2)O(2) 3 Ba(1)O(1) 3 ] 2 ) forming a (cch) 2 sequence, where c corresponds to corner-sharing and h to facesharing layers of the TiO 6 octahedra, respectively. The crystal structures of the 6H orthorhombic (space group C222 1 [17]) and 6H monoclinic phase (space group P112 1 [17]) exhibit the same stacking of the BaO 3 layers with only small shifts of the atomic positions.
The ability of the 3d transition element nickel to stabilize the hexagonal phase of BaTiO 3 at room temperature (RT) was first reported by Glaister et al. [13] in 1960. Later work on Ni-doped BaTiO 3 concerned its acceptor properties [19,20]. In that work, the valence state of Ni Ti was determined to be 2 ? by measuring the temperature-dependent magnetic susceptibility and by thermogravimetry. This oxidation state was found to be independent of the oxygen partial pressure in a wide range between 10 -15 and 1.5 Á 10 7 Pa.
As a special property of BaTiO 3 , already small amounts of Sr distinctly shift the phase transition temperature cubic-hexagonal to higher temperatures [21]. Therefore, many papers reported only on 3C-BaTiO 3 ceramics, since their specimens contained Sr, e.g., 1.7 mol% in Ref. [20]. Desu et al. determined Ni 2? as the most probable Ni defect in 3C-BaTiO 3 by binding energy calculations [22]. Much later, two articles were published on hexagonal Ni-doped BaTiO 3 [14,15], but scarce investigations on the defect chemistry-such as incorporation site and valence state of the paramagnetic Ni ion and its interaction with oxygen vacancies-were reported. By means of local probe measurements, like EPR, the nature of the Ni centers in hexagonal BaTiO 3 can be studied in detail. Previous to our paper [23], no EPR investigations on Ni-doped hexagonal BaTiO 3 were known, whereas for Ni defects in 3C-BaTiO 3 EPR investigations revealed Ni ? off-centers near the Ba 2? site [24,25].
In Ref. [23], we investigated the incorporation of Ni ions in BaTiO 3 samples of both the 3C and 6H modification. At that time, only ceramic samples were available; therefore, by means of EPR investigations on paramagnetic ions and defects with half-integral spin numbers S, only the principal values of the interaction tensors of the spin-Hamiltonian operator could be derived. As a consequence, essential information for the interpretation of the measurements and especially for the structure determination of the defects was missing. Furthermore, the EPR peaks of ions and defects with integer electron spin S in ceramic samples are particularly difficult to detect. As a result of zero-field splitting, they have strongly angle-dependent lines whose edge singularities in the powder spectra are smeared out by distributions of the fine structure parameters.
Two different EPR powder spectra denoted as Z1 and Z2 were observed in the spectra of ceramic hexagonal BaTiO 3 samples and attributed to Ni 3? (S = , low spin configuration) [23]. The nearly symmetric line Z1 with isotropic g tensor (g iso-= 2.1766 ± 0.0006) was already visible in roomtemperature spectra, and its intensity and line width are determined by the Ni concentration. Furthermore, spectrum Z1 is strongly temperature dependent: In the low-temperature range (T B 150 K), it consists of three peaks arising from an orthorhombic g-tensor.
In ceramic samples with x C 0.01, an additional anisotropic powder pattern (spectrum Z2) with three peaks corresponding to g x = 2.44 ± 0.01, g y = 2.39 ± 0.01 and g z = 2.00 ± 0.01 was observed. In the orthorhombic phase (below 222 K), the Z2 lines split, showing the occurrence of a second orthorhombic spectrum. The intensities of the respective peaks were also dependent on the Ni concentration. Depending on the doping level, only about a maximum of 5% of the nominal Ni content could be related to the spectra Z1 and Z2. On the other hand, no EPR spectra were detectable, which could be assigned to Ni 2? ions with electron spin S = 1. Therefore, in Ref. [23] we concluded that the remaining incorporated Ni must be in the EPR-silent Ni 4? state. Measurements of the magnetic susceptibility, which were later performed on the same samples, falsified this conclusion. For this reason, we extended the EPR investigations to single-crystalline Ni-doped hexagonal BaTiO 3 samples. Measurements were taken in the Q-band (34 GHz) expecting the detection of resonances of Ni 2? centers despite its large line widths (DB [ 50 G).
More recent work on Ni-doped hexagonal BaTiO 3 ceramics confirmed the majority of defects to be Ni 2? as determined by x-ray photoelectron spectroscopy (XPS) [10,26] or to be a mixture between Ni 2? and small amounts of Ni 3? as derived from extended x-ray absorption fine structure (EXAFS) measurements [27]. In the latter paper, the presence of the charge-compensating oxygen vacancy in the first coordination sphere of the Ni defect was excluded.
In the present paper, we extend the investigations on the effect of nickel doping on the defect properties of hexagonal barium titanate by systematic measurements of the magnetic moment in dependence on temperature in the concentration range between 0.5 and 2.0 mol% Ni. Furthermore, we present EPR measurements on a 2.0 mol% Ni-doped hexagonal BaTiO 3 single crystal revealing a Ni 2? center and an associate between Ni 3? and a oxygen vacancy.
Theoretical investigations [28] predict the associate Ni 2?/3? Ti(2) -V O(1) to be most stable, in which the oxygen vacancy is located in the O(1) plane connecting the face-sharing oxygen octahedra. In contrast, our current EPR data exclude the formation of this defect, in accordance with our finding in the case of Fe-doped hexagonal BaTiO 3 [29,30].

Experimental procedure
Powders with the nominal composition BaTiO 3-? 0.04 BaO ? x NiO (0.005 B x B 0.02) were prepared by the conventional mixed-oxide powder technique. After mixing (agate balls, water) and calcining (1100°C, 2 h) of BaCO 3 (Solvay, VL600, \ 0.1 mol% Sr) and TiO 2 (Merck, no. 808), NiO (Merck, p.a.) was added to the BaTiO 3 powder. Then, the mixture was fine-milled (agate balls, 2-propanol) and densified to disks with a diameter of 6 mm and a height of approximately 3 mm. The samples were sintered in air at temperatures of 1400°C for one hour (heating rate 10 K/min). A part of the sintered samples were post-annealed in flowing Ar (5 N, 40 ml/min, oxygen partial pressure approx. 0.1 Pa) at 1200°C for two hours. The Ni concentration of in the grown grains of the ceramics was measured by wavelength-dispersive X-ray electron probe microanalysis (EPMA/WDX) using a CAMEBAX (Cameca). The WDX analysis confirmed the nominal Ni content within a relative uncertainty of 10%.
Single crystals of nominal composition BaTi 0.98-Ni 0.02 O 3 were grown starting from a powder prepared by the technique described above. Rods for the growth experiments were obtained by hydrostatic pressing followed by sintering in air. Crystal growth experiments were carried out in a Crystal Systems Corporation optical floating zone furnace model FZ-T-10000-H-VPO-PC equipped with four 1500 W halogen lamps. Nitrogen (5 N purity) with a gas flow of 100 ml/min was used as atmosphere. During the crystal growth, feed and seed rods were counter-rotated with 25 rpm. The resulting crystal boules were cut into pieces of approximately 1 9 1 9 1 mm 3 with a diamond wheel saw. Single crystallinity of the samples was checked using a four-circle single-crystal diffractometer (STOE Stadi4, graphite monochromator) operating with Mo-K a radiation. This diffractometer was also used for orientation of the crystals. To describe the orientation of the crystals, we use the Cartesian laboratory co-ordinate system x L , y L , z L , which is related to the hexagonal crystallographic co-ordinate system by x L jj [100] h (= a), z L jj [001] h (= c), y L perpendicular to x L and z L ., i.e., jj [120] h (the index h refers to the hexagonal crystal system). For EPR investigations, a sample with [210] h orientation (with an accuracy B 1°) was glued to a high-purity quartz rod. With this orientation, a rotation in the crystallographic bc-plane is achieved.
Magnetic measurements were taken using the ACMS magnetometer option of a PPMS 9 (Quantum Design). The temperature-dependent magnetic moments were measured at maximum accessible field of 90 kOe in the temperature range of 5-300 K using field-cooled (FC) and zero-field-cooled (ZFC) conditions. The obtained magnetic moments were corrected for the magnetic moment of the sample holder and with respect to the magnetic contribution of the BaTiO 3 matrix, which was determined from undoped samples.
Single-crystal EPR measurements were taken with a Bruker EMX spectrometer (Q-band 34.0 GHz) with 100 kHz field modulation using a cylindrical cavity ER 5106 QT (TE 012 ) in connection with an Oxford Instruments cryostat CF 935. The microwave frequencies were determined by an electronic frequency counter. The angular dependences of the resonance fields were measured by rotating the single crystals in steps of 5°around the [210] h -axis.
Both the spectra of the single crystal and their angular dependences were evaluated using the MATLAB 1 toolbox for electron paramagnetic resonance 'EasySpin 5.2.27 0 and the toolbox 'Optimization' [31]. For evaluating the spectral parameters of the Ni defects, the spin Hamiltonian are used for spin-1/2 (Ni 3? ) and spin-1 (Ni 2? ) centers, respectively [32] (l B is Bohr's magneton, B the static magnetic field, g ¼ the g-tensor,Ŝ the electron spin operator, D the axial fine structure parameter). The characteristics of single-crystal EPR spectra (number of lines, angular dependence of the resonance fields and their intensities) of Ni 2? ions with the electron spin S = 1 are essentially determined by the size of the zero-field splitting (ZFS; equals D in the case of S = 1) compared to the energy of the microwave photons used and by the direction of the static magnetic field with respect to the crystallographic axes. There are basically three different resonances, which are assigned to the two allowed transitions (DM S ¼ AE1) and the forbidden one (DM S ¼ AE2). In the case jDj \hf (h is Planck's constant and f the frequency of the microwave field), all three resonances can be observed. The intensity of the line belonging to the forbidden transition shows a strong angular dependence and vanishes if B is parallel to the symmetry axis in the case of an axial ZFS.
If jDj [ hf only the forbidden transition can be excited, so that only one single line with strong angledependent intensity appears for certain orientations of B in the spectrum (see ''Spectra related to Ni 2? '' section).

Results and discussion
Magnetic susceptibility of ceramic samples  [30]. Hence, we also assume an AFM interaction between paramagnetic Ni ions reducing the magnetic susceptibility at higher Ni concentrations. In our previous work [23], we found by EPR measurements that only about 5% of the nominal Ni content of the samples forms Ni 3? ions and we proposed that the remaining nickel ions are in the 4? valence state, since no Ni 2? resonances could be detected in the ceramic samples. The following analysis of the susceptibility data shows that this assumption is most likely not valid and the remaining Ni is in the 2? valence state. By annealing the samples in reducing Ar atmosphere, the concentration of Ni 3? ions is decreased to about 3% of its value before annealing [23], thus transforming practically all Ni into the 2? valence state. Therefore, only the data of the Ar-annealed samples are evaluated in the following. The molar magnetic susceptibilities of all annealed samples in the entire concentration range from 0.5 to 2.0 mol% are very similar within the measurement accuracy. The fact that also the samples with a higher Ni content exhibit the same susceptibility (in contrast to the air-sintered counterparts) can be explained by the distinct increase in the concentration of oxygen vacancies due to the treatment in reducing atmosphere (with an oxygen partial pressure of about 0.1 Pa). The AFM interaction reducing the susceptibility of the air-sintered samples (x = 0.015, 0.020) is caused by superexchange via bridging oxygen ions [30]. Hence, the decreased concentration of oxygen ions upon Ar annealing reduces the AFM interaction.
The n eff (T) plot [33,34] for all annealed samples is shown in Fig. 2. The effective number n eff of Bohr magnetons l B of the paramagnetic ion is given as Comparing the n eff data with the spin-only values for S = , S = 1 and S = 3/2 clearly show the prevailing presence of Ni 2? ions (S = 1) in the annealed (and also as-sintered) samples. The deviation from the spin-only value is caused by the ground term A 2g (cubic crystal field, point group O h ) or A 2 (trigonal crystal field, point group C 3v ) of the d 8 (Ni 2? ) configuration. The spin-only formula is a good approximation only for the d 5 configuration (e.g., Fe 3? ) with ground term A 1g or A 1 [33]. For ground states A 2g and A 2 , the paramagnetic susceptibility is characterized by an additional temperature-independent term causing the deviation from the spin-only formula.
A further proof of Ni 2? ions as the majority defect species both in air-sintered and in Ar post-annealed samples is the fitting of v mol by the program CON-CORD [35] using the ligand field approach. Details of the program can be found, for example, in [36]. A successful fit of the molar susceptibility was only possible assuming the formation of Ni 2? ions, as shown in Fig. 3. The experimental data cannot be  described reasonably with Ni 3? or Ni 4? ions, which is demonstrated by applying different values for the octahedral crystal field parameter B 4 0 (Wybourne notation [37]) as also shown in Fig. 3. The B 4 0 values for the calculation by CONCORD are taken near the transition between high spin and low spin behavior. In hexagonal BaTiO 3 , the local symmetry of the oxygen octahedra at the Ti(1) site is D 3d and at the Ti(2) site it is C 3v . Therefore, the calculations should better be performed in the framework of a trigonal crystal field. On the other hand, the influence of the additional trigonal crystal field component (parameters B 2 0 , B 4 3 ) on the molar susceptibility is so weak that an adequate fitting is possible already by a cubic crystal field with B 4 0 = -17,300 cm -1 (co-ordinate system with hexagonal c-axis as z-axis). As described in ''Spectra related to Ni 2? '' section below, the addition of further experimental data from EPR measurements is needed for the estimation of the trigonal parameters.

Q-band EPR investigations on single crystals
Spectra related to Ni 3? Figure 4a shows the Q-band EPR spectrum of the Nidoped crystal with the static magnetic field B parallel to the hexagonal c-axis. Since the single-crystalline sample was grown under reducing atmosphere (see ''Experimental procedure'' section) strongly decreasing the concentration of Ni 3? [23], the intensity of the Ni 3? lines is comparatively low. Dominant in this spectrum are the fine structure lines of the isolated Fe 3? ions, which are present in our crystals as an impurity of the starting materials. These lines are very sharp because of the very low Fe concentration of B 70 ppm [29]. The spectrum of the Fe-V O associate [29] was also detectable but lies outside the magnetic field range shown. The presence of further paramagnetic impurities (Mn, Cr) leads to the resonances near the central fine structure line of the isolated Fe 3? ions.
The line of the Ni 3? center (Z1), already found in our investigations of ceramic samples [23], can easily be identified in the single-crystal spectrum due to its g-factor. The correspondence with the g-factor of spectrum Z1 of the ceramics concerns both its absolute value and its symmetry at RT, which is isotropic for the ceramics [23]. Accordingly, the resonance field of the spectrum Z1 is angle independent when the crystal is rotated around the [2 1 0] h axis (see Fig. 5). According to our previous work [23], spectrum Z1 is caused by Ni 3? surrounded by a complete oxygen octahedron without vacancy and located either on Ti(1) or on Ti(2) site. Its g-value is given in Table 1.
A second Ni 3? related spectrum, denoted as Z2, also consists of only one line for Bjjc. It overlaps with   Table 1. the fine structure line M S = 3/2 $ M S = 1/2 of the Fe 3? spectrum and is therefore barely visible. If the direction of the static magnetic field deviates from the hexagonal c-direction, this spectrum becomes clearly visible and consists of an angle-dependent triplet (Fig. 4b). Also spectrum Z2 was already detected in ceramic samples. Like Z1 it was assigned to Ni 3? ions possessing low-spin configuration with S = (3d 7 , strong octahedral field approximation). These ions are located at the other Ti site compared to the Ni 3? ions causing Z1 [23]. The angle dependence of spectrum Z2 found for the single crystal (see Fig. 5) now reveals that the previous assumption concerning the location within an intact oxygen octahedron is wrong. A qualitatively analogous angular dependence was already observed in the case of iron-doped hexagonal BaTiO 3 caused by an associate between Fe 3? and a vacancy in the surrounding oxygen octahedron (see Fig. 5 in [29]). The symmetry of the angular dependence can easily be understood by the six possible positions of the associate in each Ti(1)O 6 or Ti(2)O 6 unit. For B jj c, all six associate positions are equivalent, whereas for B jj b = [0 1 0] h four positions cause a resonance field of 10.96 kG and the remaining two positions a resonance field of 9.94 kG, which is illustrated in Fig. 9 of [29] by a sketch of the TiO 6 unit in relation to the rotation axis [2 1 0] h . This scenario of a Ni 3? -V O associate is confirmed by the simulation/fitting of the angular dependencies shown in Fig. 5, resulting in the principal g-values and the directions of the principal axes of the g-tensors. The principal axis system for one of the six possible Z2 defect positions corresponds to a rotation of the Cartesian laboratory coordinate system x L , y L , z L around the axis x L by the angle 56.7°. The principal axis systems of the other five hexagonal symmetryrelated positions are created by rotation around the hexagonal c-axis (rotation angle 120°and 240°) and reflection on the x L -y L -plane. The principal values of the orthorhombic g-tensor for the Ni 3? center Z2 are given in Table 1. Since its principal axis systems are tilted against the hexagonal c-axis by 56.7°(respectively, 123.3°as the supplementary angle), the Ni 3? ion cannot be surrounded by an intact oxygen octahedron with trigonal symmetry. In this case, one would expect an axial g-tensor with the c-axis as the trigonal axis. Hence, the Ni 3? center is associated with a next neighbor oxygen vacancy (V O ) strongly disturbing the local symmetry at the Ni 3? site. The missing oxygen ion induces a very strong axial field, which symmetry axis lies in the Ni 3? -V O direction. But the global hexagonal lattice symmetry reduces the local symmetry at the Ni 3? ion to an orthorhombic one, which differs only slightly from the axial symmetry. Due to the two non-equivalent Ti sites in the hexagonal BaTiO 3 lattice, there are several possibilities for the formation of such associate centers, which were also detected in Fe-doped hexagonal BaTiO 3 [29,30]. If the exclusively corner-sharing octahedron is affected, the oxygen vacancy can be located at each of the six equivalent O(2) sites surrounding the Ti(1). Because the Ni 3?
Ti(1) -V O(2) distances are equal in the octahedron (and therefore also the total strength of the electrical field at the Ni site in the differently oriented associate centers), only one kind of associate centers (type 1) is expected. Because of the six possible orientations of the Ni 3?
Ti(1) -V O(2) associates in the crystal, type 1 generates generally six sets of EPR spectra in single-crystal experiments, which number, however, is reduced to three by the crystal symmetry.
A possible location of the Ni 3? -V O associate in the face-sharing octahedra causes a more complex situation. In this case, two different Ti-O distances exist due to the local 3m symmetry of the 4f position: three shorter distances R Ti(2)-O(2) = 1.958 Å and three longer ones R Ti(2)-O(1) = 1.992 Å . 2 Therefore, two kinds of Ni 3? -V O associates (type 2 and 3) are expected and the g-tensors for the two types should Table 1 Spin-Hamiltonian parameters of Ni centers in hexagonal 6H-BaTiO 3 single crystals evaluated from room-temperature Q-band spectra. H is the angle between the g z eigenvector and the hexagonal c-axis differ. The EPR spectra of type 2 and 3 have the same symmetry properties with respect to the rotation pattern as those of type 1. If structurally different Ni 3? -V O centers (type 1-3) possess almost equal gtensors, the line separation of different spectral types should be easier detected in the Q-band than in the Xband spectra. Unfortunately, in the Q-band spectra of the Z2 center, no splitting (average line width about 50 G) was observed. From this finding, it can be concluded that either the differences in the principal values of the g-tensors are smaller than Dg ¼ 5 Á 10 À2 or there is only one type of Ni 3? -V O associate.
Since the principal g-values of Z2 differ only slightly from axial symmetry (Table 1), it can be concluded that the strength of the trigonal component of the local crystal field is smaller than the field induced by the formation of the oxygen vacancy. Hence, the total field is nearly axial symmetric with the direction of one of the Ti-O bonds as its symmetry axis. This direction corresponds to the principal axis of the eigenvalue 2.02 of the g-tensor, since the other two eigenvalues are approximately identical and different from this value. The corresponding angle of the Ti (1) (Table 2). Both values differ only slightly from the experimentally observed value of 56.7°. We therefore conclude that the Ni 3? -V O associate is formed either as Ni 3þ Tið1Þ À V Oð2Þ or as Ni 3þ Tið2Þ À V Oð2Þ . The third possibility Ni 3þ Tið2Þ À V Oð1Þ can be ruled out as it would lead to an angle of 47.5°( Table 2). In that case, the oxygen vacancy would be located in the O(1) plane between the Ti(2) sites of the Ti 2 O 9 units. This finding completely corresponds to our investigations in hexagonal Fe-doped BaTiO 3 also detecting only one Fe 3? -V O associate and proposing the same possible locations as in the present work [29,30].

Spectra related to Ni 2?
Besides the spectra discussed so far, an additional broad line was observed in the range 5800-17,500 G. Systematic measurements in the entire field range of the Q-band spectrometer showed that this signal vanishes for B jj c. Its resonance field, line width and intensity are strongly dependent on the rotation angle around the [2 1 0] h axis. In Fig. 6, room-temperature spectra for different orientations are shown, and in Fig. 7 the corresponding resonance fields are depicted as a function of the rotation angle. Because our Qband spectrometer has a maximum static magnetic field strength of 18 kG, the resonance fields could not be determined for rotation angles above 75°. Due to the observed angle dependence, we assign Ni 2? ions (S = 1) to this spectrum and describe it by an axial spin Hamiltonian operator (2). The fitting of the experimental angular dependence of the resonance field B res resulted in the spin Hamiltonian parameters g = 2.20 and D = 3.55 cm -1 ( Table 1). The expected anisotropy of the g-tensor could not be resolved because of the rather high line width. The zero-field splitting (equals D in the case of S = 1) of 3.55 cm -1 is greater than the Q-band microwave photon energy of 1.134 cm -1 (f = 34.0 GHz). In turn the allowed transitions DM S ¼ AE1 cannot be detected with our Qband spectrometers. This situation is illustrated in Fig. 8 showing the magnetic field dependence of the three lowest electron energy eigenvalues (M S = -1, 0, ?1) calculated by CONCORD [35] for a ZFS of 3.55 cm -1 , an angle of 20°between B and c (corresponding to the black line EPR spectrum in Fig. 6) and for two different values for B 2 0 . The sign of B 2 0 corresponds to the kind of trigonal distortion of the oxygen octahedron. B 2 0 [ 0 represents an elongation in c-direction, which is the case for the Ti(2) site in undoped BaTiO 3 , whereas the compressed octahedron at the Ti(1) site leads to B 2 0 \ 0. In both cases, the Q-band photon energy of 1.134 cm -1 cannot induce allowed transitions. Only the forbidden transition M S = -1 $ ?1 can be observed and identified by its peculiarities, namely the very strong angle dependence of the line width and intensity. Due to the strong angle dependence of the magnetic resonance field in connection with the rather weak signal and the large line width, it was not possible to identify this peak in our previous EPR investigation on ceramic samples, leading to a wrong interpretation of the  [38]. H is the angle between Ti-O directions and the hexagonal c-axis (z L ) Ti (1) (2). This information can in principle be used to identify the site related to the different EPR spectra [29,39]. In the present case, however, unfortunately only one very broad line is observed. Moreover, it is possible that the different influence of the oxygen surroundings of the Ti(1) and Ti(2) sites on the D value is small compared to its very high value of 3.55 cm -1 . Hence, the observed broad line could be caused by overlapping signals of Ni 2? ions located at both positions Ti(1) and Ti (2). The capability of the program CONCORD to also fit eigenvalue differences DE between energetically lowest microstates can be used to fit the experimental D value. On the other hand, in the case of a trigonal crystal field with three parameters B 4 0 , B 2 0 and B 4 3 the system is underdetermined if only one experimental parameter D is available. Hence, we tried to fit the crystal field parameters using both D and the v mol (T) data simultaneously. This procedure becomes   Table 1. Rotation axis is the [2 1 0] h axis. possible by applying the advanced nonlinear fitting tool of the program ORIGIN [40] in co-operation with CONCORD. In the case of Ni 2? ions, the dependence of v mol (T) on the parameters B 2 0 and B 4 3 is quite weak as discussed in ''Magnetic susceptibility of ceramic samples'' section. For this reason, a successful simultaneous fit was only possible upon fixing of B 4 0 to the value of -17,300 cm -1 used above in the fitting of the v mol (T) data with a cubic crystal field. The resulting trigonal crystal field parameters amount to B 2 0 & 2500 cm -1 and B 4 3 & 19,000 cm -1 with an uncertainty of about 30%. On the other hand, the fit of the experimental data of D and v mol (T) is also possible using a negative value of B 2 0 of the same magnitude. Hence, the determination of the correct incorporation site (Ti(1) or Ti (2)) is actually not possible.

Conclusions
Temperature-dependent measurements of the molar paramagnetic susceptibility of Ni-doped hexagonal 6H-BaTiO 3 ceramics (0.5-2.0 mol% Ni) sintered in air at 1400°C prove that the majority of the Ni ions is in the 2? valence state. At Ni concentrations of C 1.5 mol%, a weak antiferromagnetic interaction between the Ni 2? ions is found. Room-temperature, angledependent EPR Q-band measurements on a 2.0 mol% Ni-doped single crystal revealed an associate between Ni 3? and a neighboring oxygen vacancy. Comparing the directions of the main axes of the gtensor of this associate with the directions of the Ti-O bonds in the hexagonal BaTiO 3 structure, oxygen vacancies at the O(1) site can be ruled out. Moreover, the existence of additional Ni 3? ions, which are not associated with oxygen vacancies and located at Ti (1) or Ti(2) sites, was confirmed. This already known defect type [23] was identified by its isotropic gvalue. Finally, angle-dependent EPR single-crystal measurements also revealed a further Ni 2? defect, which could not be observed in previous investigations on ceramic samples [23]. Due to its very high ZFS of 3.55 cm -1 , only the forbidden transition DM S ¼ AE2, which possesses a low signal intensity, can be observed. Because of the angle-dependence peculiarities for this forbidden transition, its broad line could be detected only for angles between the static magnetic field and the c axis in the range between 20°and 75°. A simultaneous fit of the temperature-dependent susceptibility and the EPR fine structure parameter D of the Ni 2? spectrum allowed the estimation of the parameters of the trigonal crystal field to B 4 0 & -17,300 cm -1 , B 2 0 & 2500 cm -1 and B 4 3 & 19,000 cm -1 . Since only one and rather broad Ni 2? line could be detected, no information on the location of the Ni 2? ion (Ti(1) or Ti(2)) can be given. It is also possible that the line is caused by nickel ions positioned on both sites.