1. Introduction
Ca
3NbGa
3Si
2O
14 (CNGS) single crystal with an ordered langasite-type structure has been investigated as a piezoelectric material for some applications [
1,
2,
3,
4,
5,
6,
7,
8,
9,
10]. One of the expected applications is a combustion sensor in an engine of car or ship due to the relatively high piezoelectric constant and electromechanical coupling factor at high temperature. In addition, the electrical resistivity at high temperature of CNGS single crystal is higher than that of present crystals with a disordered langasite-type structure as represented by La
3Ta
0.5Ga
5.5O
14 (LTG), La
3Nb
0.5Ga
5.5O
14 (LNG), and La
3Ga
5SiO
14 (LGS) single crystals [
5]. In recent years, the CNGS crystals have also been investigated as an oscillator for the growing demand of the oscillator with small-size and low power consumption in low frequency range [
6]. The temperature coefficient of frequency (TCF) on CNGS crystal is comparable to that of quartz along with the lower crystal impedance than quartz. Therefore, the CNGS crystal is expected to achieve the small-size oscillator with low power consumption in low frequency range. In our previous report, piezoelectric constant of an X-cut specimen was reported for the CNGS single crystal [
7]. The piezoelectric constant
d11 of the X-cut CNGS specimen was 3.98 pC/N and it was almost twice larger than that of quartz. The
d11 was constant from room temperature to more than 500 °C and it is expected to be used at such high temperature that the quartz could not be applied. In addition, the TCF of a −24.5° Y-cut CNGS crystal in a temperature range from −10 °C to 70 °C were 60 ppm and it was smaller than that of the LGS crystal [
6]. The great TCF of the CNGS crystal comparable to the AT-cut α-quartz is suitable for some applications as represented by the oscillator and the resonator.
We have developed shape-controlled langasite-type piezoelectric crystals by a micro-pulling-down (µ-PD) method [
7,
8,
9,
10,
11]. The µ-PD method can control a shape of grown crystal using a special-shaped crucible [
12] while conventional methods such as Czochralski (Cz), Bridgman-Stockbarger (BS), Floating Zone (FZ) and Flux methods cannot grow shape-controlled crystals. By the µ-PD method with special-shaped Pt crucibles, columnar, plate and tube-shaped langasite-type crystals have been grown and the shape-controlled langasite-type crystals were comparable in crystal quality and piezoelectric properties to CNGS crystals which were grown by Cz method. The near-net-shape growth of single crystal enables us to make piezoelectric elements with a configuration of final device element for each application and it can decrease costs of forming processes such as cutting and polishing after crystal growth. In addition, the µ-PD method can grow a single crystal with approximately 10 times faster growth rate than the conventional methods and it is also suitable for the material research of single crystal.
Effects of Al substitution to Ga site in langasite-type crystals with the disordered structure have been investigated [
13,
14,
15,
16,
17]. In the case of LTG, LNG and LGS crystals with the disordered structure, a portion of Ga site can be substituted by Al ion and some piezoelectric properties such as electrical resistivity and piezoelectric constants were improved by the Al doping. In contrast, as for the CNGS crystal, there are reports only about full substitution for Ga sites by Al ions [
5] and there is no detailed description about the Al concentration dependence of crystal growth, phase, crystal structure, chemical composition and physical properties for Al doped CNGS crystals. Especially in the case of the application for oscillator, the stability of TCF is one of the most important factors and the stability of TCF relates to more than one physical constant. Therefore, there is a possibility that Al doped CNGS crystal with a specific Al concentration indicates most suitable TCF for the application of oscillator.
In this study, we grew Al doped CNGS crystals with various Al concentrations by the µ-PD method and effects of Al doping on crystal growth, phase, crystal structure, chemical composition and electrical resistivity were investigated to clarify the effects of Al substitution on crystal growth, phase formation, segregation of cations and electrical resistivity at high temperature.
3. Results and Discussion
Liquid-solid interface was flat and stable just below the nozzle of crucible during crystal growth. Thickness of the melt between the liquid-solid interface and the bottom of the nozzle was approximately 100~200 µm. In the result, CNGAS crystals with a diameter of 5 mm and a length of several centimeters were obtained as shown in
Figure 1a. The as-grown CNGAS crystals with
x = 0.2, 0.4 and 0.6 indicated orange-color. The orange-color of the grown crystals is considered to be due to the oxygen defects. In our previous report about the effects of growth atmosphere for CNGS crystal, we reported the orange-color of grown crystal originated from the absorption around 300 nm in the transmittance spectrum [
18]. On the other hand, as-grown crystals with
x = 0.8 and 1 included milky parts in the crystals. The polished CNGAS crystals with
x = 0.2, 0.4 and 0.6 were transparent while the crystals with
x = 0.8 and 1 were opacity.
Powder XRD patterns of the as-grown CNGAS crystals were measured in order to investigate their phases and lattice parameters as it is illustrated in
Figure 2a. All diffraction peaks in the XRD patterns of the CNGAS crystals with
x = 0.2, 0.4 and 0.6 were indexed by the langasite-type structure and any secondary phases were not observed. In contrast, the XRD patterns of the CNGAS crystals with
x = 0.8 and 1 included some secondary phases in addition to the langasite-type phase. Lattice parameters,
a- and
c-axes lengths, of langasite-type phases in the
x range of 0.2~0.8 could be calculated from the XRD patterns (
Figure 2b)
a- and
c-axes lengths systematically decreased with an increase of Al concentration and the result suggests that Ga sites in CNGAS crystals were substituted by Al ions with smaller ionic radius than Ga ion.
Figure 1.
(a) As-grown Ca3Nb(Ga1-xAlx)3Si2O14 crystals grown by the micro-pulling-down (µ-PD) method; (b) Polished plate-like crystals cut from the as-grown Ca3Nb(Ga1−xAlx)3Si2O14 (CNGAS) crystals.
Figure 1.
(a) As-grown Ca3Nb(Ga1-xAlx)3Si2O14 crystals grown by the micro-pulling-down (µ-PD) method; (b) Polished plate-like crystals cut from the as-grown Ca3Nb(Ga1−xAlx)3Si2O14 (CNGAS) crystals.
Figure 2.
(a) Powder XRD patterns of the Ca3Nb(Ga1−xAlx)3Si2O14 crystals; (b) Lattice parameters, a- and c-axes lengths, of langasite-type phases for the CNGAS crystals calculated from the powder XRD patterns.
Figure 2.
(a) Powder XRD patterns of the Ca3Nb(Ga1−xAlx)3Si2O14 crystals; (b) Lattice parameters, a- and c-axes lengths, of langasite-type phases for the CNGAS crystals calculated from the powder XRD patterns.
Cross-sectional surfaces of the polished CNGAS crystals were observed by SEM with BSE (
Figure 3a). For the CNGAS crystals with
x = 0.2, 0.4 and 0.6, only one phase was observed in the BSE images and the result is consistent with the results of powder XRD patterns. In contrast, there were three phases in the BSE images of the CNGAS crystals with
x = 0.8 and 1. Chemical compositions of their phases were analyzed by EPMA, and actual Al and Ga concentrations of the langasite-type phase in the CNGS crystals with
x = 0.2, 0.4, 0.6 and 0.8 were illustrated in
Figure 3b. Actual Al concentrations in the CNGAS phases were systematically increased and Ga concentrations were decreased with an increase of Al concentration in the nominal compositions. In the case of
x = 0.8 and 1, gray areas (A in
Figure 3) were langasite-type phase and the cation ratios were almost consistent with the nominal compositions. In contrast, black (B) and white (C) areas in BSE images of the crystals with
x = 0.8 and 1 were identified by Ca-Al-Si-O and Ca-Nb-O systems, respectively. Increase of Al concentration in the CNGAS crystal generated secondary phases in the
x range of 0.8~1 while even the crystal with
x = 1 included the langasite-type phase, Ca
3NbAl
3Si
2O
14. The result suggests that the CNGAS was changed to incongruent phase from the congruent phase by the Al substitution and the change point is in the
x range of 0.6~0.8.
Figure 3.
(a) Back-Scattering electron images of cross sectional planes for polished Ca3Nb(Ga1−xAlx)3Si2O14 crystals. A, B and C were different phases; (b) Actual Ga and Al concentrations in cation elements of the langasite-type phase in the Ca3Nb(Ga1−xAlx)3Si2O14 crystals with x = 0.2, 0.4, 0.6 and 0.8.
Figure 3.
(a) Back-Scattering electron images of cross sectional planes for polished Ca3Nb(Ga1−xAlx)3Si2O14 crystals. A, B and C were different phases; (b) Actual Ga and Al concentrations in cation elements of the langasite-type phase in the Ca3Nb(Ga1−xAlx)3Si2O14 crystals with x = 0.2, 0.4, 0.6 and 0.8.
For the crystal with
x = 0.6, chemical compositions of cation elements, Ca, Nb, Ga, Al, Si, along to growth direction were investigated. The segregation fraction dependence of each cation concentration is shown in
Figure 4. All cations were almost constant with an increase of the solidification fraction. The effective solidification coefficient,
keff, of each cation was calculated by the standard segregation equation,
C = C
0keff(1 −
g)
keff − 1 (
C: cation concentration in the crystal, C
0: cation concentration of the nominal composition,
g: solidification fraction). In the result, all
keff’s of Ca, Nb, Ga, Al and Si were 1.00 and there was no segregation along to the growth direction in the grown crystal. However, actual Al concentration on Ga site in the crystal was approximately 68% and it was slightly larger than nominal composition. The essential reason for the increase of Al concentration in the grown crystal is not clear; however, there is a possibility that Ga evaporation during crystal growth increased the actual Al concentration in the crystal. The average chemical composition of grown CNGAS crystal was Ca
3.01Nb
0.95(Ga
0.32Al
0.68)
2.94Si
2.08O
14±δ. In the result, Nb and (Ga,Al) concentrations were smaller than the nominal composition while Ca and Si concentration were larger than the nominal composition. The result suggests that there are some anti-site defects among caion sites in the crystal.
Figure 4.
Chemical composition of cation elements along to growth direction for Ca3Nb(Ga0.6Al0.4)3Si2O14 crystal (x = 0.6) measured by Electron Probe Micro-Analysis (EPMA).
Figure 4.
Chemical composition of cation elements along to growth direction for Ca3Nb(Ga0.6Al0.4)3Si2O14 crystal (x = 0.6) measured by Electron Probe Micro-Analysis (EPMA).
Temperature dependences of electrical resistivities for the polished CNGAS crystals with
x = 0.4 and 0.6 were described in
Figure 5 and the electrical resistivity of undoped crystal was added by way of comparison. Clear difference in the electrical resistivities between CNGS and CNGAS crystals was not observed while Al substitution increased the electrical resistivity in the case of langasite-type crystals with the disordered structure [
15].
Figure 5.
Temperature dependence of electrical resistivities for the Ca3Nb(Ga1−xAlx)3Si2O14 crystals with x = 0.4, 0.6 and undoped CNGS crystals.
Figure 5.
Temperature dependence of electrical resistivities for the Ca3Nb(Ga1−xAlx)3Si2O14 crystals with x = 0.4, 0.6 and undoped CNGS crystals.