Structural parameters of AgNbO3 at
1. Introduction
Many ferroelectric oxides possess the ABO3 perovskite structure (Mitchell, 2002), in which the A-site cations are typically larger than the B-site cations and similar in size to the oxygen anion. Figure 1 shows a schematic drawing for this structure, where the A cations are surrounded by 12-anions in the cubo-octahedral coordination and the B cations are surrounded by 6-anions in the octahedral coordination. An ideal perovskite exhibits a cubic space group
where
Although BaTiO3- and PbTiO3-based ceramics materials have been widely used in electronic industry (Uchino, 1997; Scott, 2000), there remain some importance issues to be solved. One of such challenges is to seek novel compounds to replace the Pb-based materials, which have a large Pb-content and raises concerns about the environmental pollution (Saito et al.,2004; Rodel et al.,2009 ).
The discovery of extremely large polarization (52 µC/cm2) under high electric field in the AgNbO3 ceramics (Fu et al., 2007) indicates that Ag may be a key element in the designs of lead-free ferroelectric perovskite oxides (Fu et al., 2011a). With the advance of first-principles calculations (Cohen, 1992) and modern techniques of synchrotron radiation (Kuroiwa et al., 2001), we now know that the chemical bonding in the perovskite oxides is not purely ionic as we have though, but also possesses covalent character that plays a crucial role in the occurrence of ferroelectricity in the perovskite oxides (Cohen, 1992; Kuroiwa et al., 2001 ). It is now accepted that it is the strong covalency of Pb with O that allows its large off-center in the A-site. Although Ag doesn’t have lone-pair electrons like Pb, theoretical investigations suggest that there is hybridization between Ag and O in AgNbO3(Kato et al., 2002; Grinberg & Rappe, 2003,2004), resulting in a large off-center of Ag in the A-site of perovskite AgNbO3 (Grinberg & Rappe, 2003,2004). This prediction is supported by the results from X-ray photoelectron spectroscopy, which suggest some covalent characters of the chemical bonds between Ag and O as well as the bonds between Nb and O (Kruczek et al., 2006). Moreover, bond-length analysis also supports such a theoretical prediction. Some of the bond-lengths (~2.43 Å) in the structure (Sciau et al., 2004; Yashima et al. 2011) are significantly less than the sum of Ag+ (1.28 Å) and O2- (1.40 Å) ionic radii (Shannon, 1967). All these facts make us believe that AgNbO3 may be used as a base compound to develop novel ferroelectric materials. Along such a direction, some interesting results have been obtained. It was found that ferroelectricity can be induced through the chemical modification of the AgNbO3 structure by substitution of Li (Fu et al., 2008, 2011a), Na(Arioka, 2009; Fu et al., 2011b), and K (Fu et al., 2009a) for Ag. Large spontaneous polarization and high temperature of para-ferroelectric phase transition were observed in these solid solutions. In the following sections, we review the synthesis, structure, and dielectric, piezoelectric and ferroelectric properties of these solid solutions together with another silver perovskite AgTaO3 (Soon et al.,2009, 2010), whose solid solutions with AgNbO3 are promising for the applications in microwaves devices due to high dielectric constant and low loss (Volkov et al. 1995; Fortin et al., 1996; Petzelt et al., 1999; Valant et al., 2007a).
2. AgNbO3
2.1. Synthesis
Both single crystal and ceramics of AgNbO3 are available. Single crystal can be grown by a molten salt method using NaCl or V2O5 as a flux (Łukaszewski et al., 1980; Kania, 1989). Ceramics samples can be prepared through a solid state reaction between Nb2O5 and silver source (Francombe & Lewis, 1958; Reisman & Holtzberg, 1958). Among the silver sources of metallic silver, Ag2O and Ag2CO3, Ag2O is mostly proper to obtain single phase of AgNbO3(Valant et al., 2007b). For silver source of Ag2O, thermogravimetric analysis indicates that phase formation can be reach at a firing temperature range of 1073-1397 K (Fig. 3). The issue frequently encountered in the synthesis of AgNbO3 is the decomposition of metallic silver, which can be easily justified from the color of the formed compounds. Pure powder is yellowish, while grey color of the powder generally indicates the presence of some metallic silver. It has been shown that the most important parameter that influences the phase formation is oxygen diffusion (Valant et al., 2007b). In our experiments to prepare the AgNbO3 ceramics, we first calcined the mixture of Ag2O and Nb2O5 at 1253 K for 6 hours in O2 atmosphere and then sintered the pellet samples for electric measurements at 1323 K for 6 hours in O2 atmosphere (Fu et al., 2007). Insulation of these samples is very excellent, which allows us to apply extremely high electric field to the sample (Breakdown field >220 kV/cm. For comparison, BaTiO3 ceramics has a value of ~50 kV/cm.)
2.2 Electric-field induced ferroelectric phase
Previous measurements on
2.3. Room-temperature structure
There are many works attempting to determine the room-temperature structure of AgNbO3 (Francombe & Lewis, 1958; Verwerft et al., 1989; Fabry et al., 2000; Sciau et al., 2004; Levin et al., 2009). However, none of these previous works can provide a
|
||||
Site |
|
|
|
|
Ag1 4 |
0.7499(3) | 0.7468(3) | 0.2601(5) | 0.0114(2) |
Ag2 2 |
1/2 | 0.7466(6) | 0.2379(5) | 0.0114(2) |
Ag3 2 |
0 | 0.7424(4) | 0.2759(6) | 0.0114(2) |
Nb1 4 |
0.6252(2) | 0.7525(5) | 0.7332(2) | 0.00389(18) |
Nb2 4 |
0.1253(2) | 0.24159 | 0.27981 | 0.00389(18) |
O1 4 |
0.7521(9) | 0.7035(12) | 0.7832(24) | 0.0057(5) |
O2 2 |
1/2 | 0.804(3) | 0.796(3) | 0.0057(5) |
O3 4 |
0.6057(7) | 0.5191(18) | 0.4943(18) | 0.0057(5) |
O4 4 |
0.6423(7) | 0.0164(18) | 0.539(2) | 0.0057(5) |
O5 2 |
0 | 0.191(3) | 0.256(3) | 0.0057(5) |
O6 4 |
0.1339(9) | 0.0410(17) | 0.980(2) | 0.0057(5) |
O7 4 |
0.1154(8) | 0.4573(17) | 0.5514(19) | 0.0057(5) |
On the basis of this space group, M. Yashima (Yashima et al., 2011) exactly determined the atom positions (Table 1) in the structure using the neutron and synchrotron powder diffraction techniques. The atomic displacements are schematically shown in Fig.7. In contrast to the reported centrosymmetric
2.4. Dielectric behaviours and phase transitions
Initial works on the phase transitions of AgNbO3 and their influence on the dielectric behaviors were reported by Francombe and Lewis (Francombe & Lewis, 1958) in the late 1950s, which trigger latter intensive interests in this system (Łukaszewski et al., 1983; Kania, 1983, 1998; Kania et al., 1984, 1986; Pisarski & Dmytrow, 1987; Paweczyk, 1987; Hafid et al., 1992; Petzelt et al., 1999; Ratuszna et al., 2003; Sciau et al., 2004). The phase transitions of AgNbO3 were associated with two mechanisms of
AgNbO3 | |||||
Atom | 573 K | 645 K | 733 K | 903 K | |
Nb |
|
0.2460(15) | 1/4 | 0 | 0 |
|
0.2422(10) | 1/4 | 0 | 0 | |
|
0.1256(6) | 0 | 0 | 0 | |
|
1.12(6) | 1.31(4) | 1.38(4) | 1.63(2) | |
Ag(1) |
|
-0.2507(35) | 0 | 0 | 1/2 |
|
1/4 | -0.001(2) | 1/2 | 1/2 | |
|
0 | 1/4 | 1/2 | 1/2 | |
|
2.78(7) | 1.98(6) | 2.80(3) | 3.47(4) | |
Ag(2) |
|
-0.2556(26) | 0 | ||
|
0.2428(18) | 0.494(3) | |||
|
1/4 | 1/4 | |||
|
1.73(6) | 3.54(8) | |||
O(1) |
|
0.3022 | 0.2827(7) | 0 | 0 |
|
1/4 | 1/4 | 0 | 0 | |
|
0 | 0 | 1/2 | 1/2 | |
|
1.31(6) | 2.27(5) | 3.14(5) | 3.60(4) | |
O(2) |
|
-0.0292(14) | 0 | 0.2782(3) | |
|
0.0303(14) | 0.2259(8) | 0.2218 | ||
|
0.1140(6) | 0.0205(8) | 0.0358(4) | ||
|
1.71(7) | 1.94(4) | 2.08(4) | ||
O(3) |
|
0.5262(13) | 0.2710(7) | ||
|
0.4778(14) | 0.2456(11) | |||
|
0.1375(5) | 1/4 | |||
|
1.17(6) | 2.56(6) | |||
O(4) |
|
0.2155(23) | |||
|
0.2622(24) | ||||
|
1/4 | ||||
|
1.67(7) | ||||
cell |
|
5.5579(5) | 7.883(1) | 5.5815(3) | 3.9598(3) |
|
5.5917(6) | 7.890(1) | |||
|
15.771(2) | 7.906(1) | 3.9595(3) |
is not so visible. However, it can be easily ascertained in the differential curve or in the cooling curve. This anomaly is nearly unnoticed in the literatures (Łukaszewski et al., 1983; Kania, 1983, 1998; Kania et al., 1986; Pisarski & Dmytrow, 1987; Paweczyk, 1987; Hafid et al., 1992; Ratuszna et al., 2003). The detailed examination of the temperature dependence of the 220o
3. (Ag1-x
Li
x
)NbO3 solid solution
Li can be incorporated into the Ag-site of AgNbO3. However, due to the large difference of ionic radius of Li+(0.92Å), and Ag+( 1.28Å)(Shannon, 1976), the solid solution is very limited. Nalbandyan
3.1. Synthesis
Single crystals of (Ag1
Ceramics samples can be prepared by a solid state reaction approach. Mixtures of Ag2O, Nb2O5, and Li2CO3 were calcined at 1253 K for 6 h in O2 atmosphere, followed by removal of the powder from the furnace to allow a rapid cooling to prevent phase separation. The calcined powder was milled again and pressed to form pellets that were sintered at 1323 K for 6 h in O2 atmosphere, followed by a rapid cooling.
3.2. Structure
The structural refinements using the powder X-ray diffraction data suggest that (Ag1
Ag0.9Li0.1NbO3 (R3c, No.161, T=room temperature) | |||||
|
5.52055(9) | α | 90 | ||
|
5.52055(9) | β | 90 | ||
|
13.7938(3) | γ | 120 | ||
V(Å3) | 364.07 | ||||
Atom | Site |
|
|
|
|
Ag/Li | 6a | 0 | 0 | 0.2545(8) | 0.5 |
Nb | 6a | 0 | 0 | 0.0097(8) | 0.5 |
O | 18b | 0.5533 | 1 | 0.2599(9) | 0.5 |
3.3. Ferroelectric and piezoelectric properties
Evolution of the polarization state in Ag1-
ferroelectric state with large value of remanent polarization (
The strain-
3.4. Dielectric behaviours and proposed phase diagram
Figure 13 shows the dielectric behaviours of the ferroelectric Ag1-
that the higher temperature phase transition is not related to a ferroelectric phase transition. On the basis of the dielectric measurements, the phase diagram of Ag1-
4. (Ag1-x
Na
x
)NbO3 solid solution
The ionic radius of Na+ (1.18 Å) is comparable to that of Ag+ (1.28 Å) (Shannon, 1976), allowing to prepare the Ag1-
4.1. Synthesis
Ag1
Composition | Temperature | Time | atmosphere |
|
1273K | 5h | O2 |
|
1323K | 5h | O2 |
|
1373K | 5h | O2 |
4.2. Polarization
Figure 15 shows the change in polarization with composition in the Ag1-
4.3. Dielectric properties
The dielectric properties of the Ag1
5. (Ag1-x
K
x
)NbO3 solid solution
(Ag1
5.1. Synthesis
(Ag1
5.2. Structural change with composition
Figure 18 shows the change in lattice parameters with composition in the Ag1
5. 3. Ferroelectric and piezoelectric properties
Figure 19 shows typical results of polarization and strain behaviors observed at room temperature for the Ag1
5.4. Dielectric behaviours and proposed phase diagram
Associating with the change in structure, dielectric behaviours of the Ag1
6. AgTaO3
AgTaO3 is another oxide of the two discovered silver perovskites (Francombe & Lewis, 1958). It is generally accepted that AgTaO3 undergoes a series of phase transitions from rhombohedral phase (
6.1. Synthesis
Although single crystal of AgTaO3 is available through a flux method (Łukaszewski et al., 1980; Kania, 1989), it is extremely difficult to prepare its dense ceramics sample (Francombe & Lewis, 1958;Kania,1983) for electrical measurements. Since decomposition of AgTaO3 occurs at 1443±3 K in atmosphere (Valant et al., 2007b), sintering cannot be performed at higher temperatures to obtain dense ceramics. However, this long-standing synthesis difficulty now can be solved by a processing route involving the conventional solid-state reaction and sintering in environment with a high oxygen pressure at ~13 atm (Soon et al., 2010). In this synthesizing route, Ag2O and Ta2O5, first underwent a grind mixing and was calcined at 1273 K for 6 hours. The calcined powder was then pressed into a pellet in 6 mm in diameter. Sintering was carried out by placing the powder compact into a sealed zirconia tube that was connected to a pressure control valve (Fig.22). Prior to the sintering, oxygen gas at ~6.25 atm was filled into the sealed zirconia tube after the evacuation. Upon heating, the pressure of sealed oxygen gas increased and reached ~13 atm when the powder compact was sintered at 1573K for 2 hours. This eventually led to formation of dense polycrystalline AgTaO3.
6.2. Phase formation and dielectric behaviors
X-ray diffraction analyses (Fig.23) suggest the AgTaO3 is rhombohedral with
Although several frequency-dependent peaks are seen in the dielectric loss (Fig.24(b)), it can be reasonably attributed to polarization relaxations due to defects (Soon et al., 2010). Interestingly, within the low-temperature region, the dielectric behavior follows the Barrett’s relation (Barrett, 1952) that is characteristic for the quantum paraelectric system (Abel, 1971; Höchli & Boatner,1979; Itoh et al., 1999), suggesting that AgTaO3 may be a quantum paraelectric. On the other hand, two step-like dielectric anomalies corresponding to the phase transitions from monoclinic to tetragonal and tetragonal to cubic were observed at 694 and 780 K, respectively, upon heating the samples (Fig.26). This observation is in agreement with the previous reports (Kania,1983;Kugel et al., 1987). Furthermore, the temperature dependence of 1/
7. (Ag1-x
Li
x
)TaO3 solid solution
Similar to the case of AgNbO3, ~12 mole% of Li can be incorporated into the Ag-site of AgTaO3 to form (Ag1
7.1. Synthesis
(Ag1-
7.2. Dielectric behaviours and confirmation of ferroelectric phase
Figures 27& 28 plot the temperature dependence of dielectric constant
On the basis of the above results, a phase diagram is proposed in Fig.31, in which PE and FE represents the paraelectric and ferroelectric phases, respectively. As mentioned above, since the peak of the dielectric constant is strongly dependent with frequency for 0<
8. Concluding remarks
Our recent works reveal that silver perovskites are of great interests from either the view-point of fundamental research or that of application research in the fields of ferroelectric or piezoelectric. Promising ferroelectric and piezoelectric properties have been demonstrated in some compounds such as (Ag,Li)NbO3 and (Ag,K)NbO3 alloys, but further works are required to improve the material performance, to understand the basic physics of the ferroelectricity/piezoelectricity of the materials, and to seek novel promising compounds among the discovered solutions or alloys with other ferroelectric systems. Moreover, integration techniques of thin films are also a direction for the future works when considering the practical applications.
Acknowledgments
Part of this work was supported by the Collaborative Research Project of Materials and Structures Laboratory of Tokyo Institute of Technology, and Grant-in-Aid for Scientific Research, MEXT, Japan.
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