Sodium, Silver and Lithium-Ion Conducting β ”-Alumina + YSZ Composites, Ionic Conductivity and Stability

: Na- β ”-alumina (Na 2 O.~6Al 2 O 3 ) is known to be an excellent sodium ion conductor in battery and sensor applications. In this study we report fabrication of Na- β ”-alumina + YSZ dual phase composite to mitigate moisture and CO 2 corrosion that otherwise can lead to degradation in pure Na- β ”-alumina conductor. Subsequently, we heat-treated the samples in molten AgNO3 and LiNO3 to respectively form Ag- β ”-alumina + YSZ and Li- β ”-alumina + YSZ to investigate their potential applications in silver- and lithium-ion solid state batteries. Ion exchange fronts were captured via SEM and EDS techniques. Their ionic conductivities were measured using electrochemical impedance spectroscopy. Both ion exchange rates and ionic conductivities of these composite ionic conductors were ﬁrstly reported here and measured as a function of ion exchange time and temperature.

Conventional process for the fabrication of Na-β"-alumina involves first calcining a mixture of alumina (Al 2 O 3 ), Na 2 CO 3 and LiNO 3 (or MgO) at 1250 • C for 2 h. This leads to the formation of a mixture of Na-β"-alumina, Na-β-alumina (Na 2 O.~11Al 2 O 3 ) and NaAlO 2 . Discs, bars or tubes are formed by powder-pressing. The samples are then placed in platinum containers or MgO containers and heated in air to~1600 • C for a few minutes and rapidly cooled to~1450 • C and heat-treated for an hour to convert Na-β-alumina into Na-β"-alumina by the reaction [13]: Sintering occurs by a transient liquid phase mechanism. Some NaAlO 2 remains at the grain boundaries, which makes the material susceptible to degradation by moisture and CO 2 present in the atmosphere. Thus, Na-β"-alumina made by conventional methods typically needs to be stored in desiccators.
A vapor phase process was originally developed by one of the authors to fabricate Na-β"-alumina-containing materials in which two phase samples of α-alumina + YSZ are fabricated by pressing and sintering [14][15][16]. The proportions of the two phases are such that both phases are contiguous. The sintered samples are then buried in Na-β"alumina powder and heat-treated at 1250 • C to 1400 • C for several hours. This leads to the conversion of α-alumina into Na-β"-alumina thus forming a two phase composite of Na-β"-alumina + YSZ. Rapid conversion occurs since the incorporation of Na 2 O occurs by a coupled transport of 2Na + through the formed Na-β"-alumina and O 2− through YSZ, which is an oxygen ion conductor [14][15][16]. The overall reaction is: In this process, NaAlO 2 is not present and thus boundaries are free of any NaAlO 2 . Such samples are resistant to degradation by moisture and CO 2 in the atmosphere. Samples of the composite are very fine-grained and thus exhibit excellent strength.
It has been known for a long time that β"-alumina is capable of transporting other alkali ions, silver ion, some divalent ions and even trivalent ions and can be made by ion exchange in which Na-β"-alumina is immersed in the respective molten salt for several hours [17][18][19][20][21]. For example, to form Ag-β"-alumina, Na-β"-alumina is immersed in molten AgNO 3 . The reaction: Na 2 O.~6Al 2 O 3 + Ag + → Ag 2 O.~6Al 2 O 3 + Na + (3) occurs to some extent. Typically, partial replacement of Na + occurs by Ag + , thus forming a silver ion-conducting β"-alumina. Many β"-alumina formed by ion exchange are kinetically stable at low temperatures because oxygen diffusion through β"-alumina is extremely sluggish. Thus, reactions such as: do not occur at low temperatures (e.g., below about 600 • C). The objective of this work was to investigate ion-exchange of Na-β"-alumina + YSZ to form Ag-β"-alumina + YSZ and Li-β"-alumina + YSZ composites. At low temperatures, below about 500 • C, oxygen ion conductivity of YSZ is much lower than sodium ion conductivity of Na-β"-alumina. Thus, the composite is essentially a sodium ion conductor. However, at elevated temperatures, the oxygen ion conductivity is significant. In samples made by ion exchange, the stability is kinetic. Thus, samples of Ag-β"-alumina + YSZ may become unstable. In order to explore this possibility, it was also the objective of this work to determine its stability at elevated temperatures.

Materials and Methods
α-Alumina (Baikowski, France) powder and 3YSZ (Tosoh, Tokyo, Japan) powder in a volume proportion of~70% and~30% were mixed and ball-milled for 12 h. Discs were uniaxially pressed followed by isostatic pressing. The discs were sintered in air at 1600 • C for 5 h. Na-β"-alumina packing powder was made by mixing Na 2 CO 3 , LiNO 3 and α-Al 2 O 3 and calcined at 1250 • C for 2 h. The composition of the powder was~8.85 wt.% Na 2 O, 0.75 wt. Li 2 O% (as stabilizer) and balance Al 2 O 3 . Sintered α-alumina + YSZ samples were buried in Na-β"-alumina powder and heat-treated at 1250 • C and 1350 • C for several hours. Samples were periodically cooled to room temperature and weighed. After each treatment, sample weight was measured to monitor the conversion of α-alumina into Na-β"-alumina. The samples were heat treated until no further weight change occurred, indicating full conversion through the thickness of the sample.
Flat surfaces of the discs were polished. The discs were then immersed in molten AgNO 3 and LiNO 3 for ion exchange to respectively form Ag-β"-alumina + YSZ and Liβ"-alumina + YSZ at 300 • C and 365 • C (in AgNO 3 ) and 300 • C and 370 • C (in LiNO 3 ). Samples were periodically removed, cooled to room temperature, washed in water to remove salt sticking to the samples, dried and weighed to determine the extent of ion exchange. Thin layers of gold were applied as a paste on the surfaces and fired at 500 • C for 1 h. Platinum mesh was placed on the two surfaces and then placed between ceramic honeycomb structures and spring-loaded. EIS was conducted over a range of temperatures. Upon removal from the fixture, the gold layers formed thin films bonded to the platinum mesh. The samples were further ion exchanged for a period of time, and weighed. In this manner, EIS measurements could be made after various ion exchange treatments, allowing a study of conductivity as a function of the degree of ion-exchange. After a certain period of time, samples were immersed in molten NaNO 3 to reverse ion exchange back to predominantly Na-β"-alumina + YSZ. EIS measurements were also made after reverse ion exchange with sodium. At these relatively low temperatures, the oxygen ion conductivity of YSZ is much lower than that of β"-alumina. Thus, the only transport occurs through the β"-alumina phase.
In order to determine the possible instability of Ag-β"-alumina at elevated temperatures, a disc of ion-exchanged sample was first weighed to the accuracy of 0.0001 g. One disk was then heated in air at 900 • C for 2 and 3 h. Another ion-exchanged disc was heated in air at 900 • C for 12 h. The samples were weighed after each treatment. After the final treatment, the sample heated for 3 h was leached in nitric acid. After drying, the sample once again was weighed.Samples were characterized using scanning electron microscopy (SEM, FEI Nova Nano, Hillsboro, USA), EDS (FEI Nova Nano, Hillsboro, USA) and X-ray diffraction (Philips PANalytical X'Pert, Amsterdam, Netherlands). Figure 1a shows an SEM micrograph of an as-converted Na-β"-alumina + YSZ sample. Figure 1b shows an SEM image of the sample after ion exchange in LiNO 3 for 24 h. No microstructural changes are observed, consistent with expectations, since the only change that occurs is the partial replacement of Na + by Li + in Na-β"-alumina. Also shown in insets are EDS scans. Lithium is too light to be detected. However, it is seen that in the partially ion-exchanged sample, the sodium count is lower, consistent with its partial replacement.   unchanged. The EDS spectrum shows peaks corresponding to O, Na, Al, Zr and Y. The intensity of the Na peak is much lower in the ion-exchanged sample consistent with its partial replacement by Li. Figure 2a shows an SEM image of a sample that had been ion-exchanged in LiNO 3 at 300 • C for 2 h. Figure 2b-d show respectively, EDS maps of O, Al and Zr. All three are uniform through the width of the image. Figure 2e shows EDS map of Na. At about 80 microns from the left, a distinct change in color is observed. Figure 2f shows actual counts of sodium. Again at~80 microns, a clear change in the sodium count is observed. This suggests that in 2 h, approximate depth of ion exchange is~80 microns. In samples not exchanged throughout the thickness, the measured conductivity reflects total conductivity which includes contributions that are spatially dependent.   Figure 3 shows EDS line scans of a sample ion-exchanged in AgNO3 at 300 °C for 1 h. The measurements were performed at near the surface region since the sample is relatively thick. At both surfaces, high concentration of silver atoms and depletion of sodium atoms are observed, indicating sodium to silver ion exchange has occurred. Away from the surface, silver concentration gradually decreases to nearly zero while Na concentration gradually recovers to a steady value reaching bulk concentration. Comparing Figures  Figure 3 shows EDS line scans of a sample ion-exchanged in AgNO 3 at 300 • C for 1 h. The measurements were performed at near the surface region since the sample is relatively thick. At both surfaces, high concentration of silver atoms and depletion of sodium atoms are observed, indicating sodium to silver ion exchange has occurred. Away from the surface, silver concentration gradually decreases to nearly zero while Na concentration gradually recovers to a steady value reaching bulk concentration. Comparing Figures 2 and 3 suggests that at the same temperature, ion exchange of Na + by Ag + can happen more rapidly, which can be understood as to be shown later as well as reported by Yao and Kummer that Na + to Ag + ion exchange has a much higher maximum ion exchange percentage (90-100%) than that of maximum Na + to Li + ion exchange (40-50%) [1]. And more importantly, even when ion-exchanged with only 10% AgNO 3 in AgNO 3 /NaNO 3 molten mixture, the maximum Na + to Ag + ion exchange percentage can exceed 80% while Na + to Li + ion exchange percentage remains less than 10% in 80% LiNO 3 in LiNO 3 /NaNO 3 molten mixture [1].

Microstructure, Elemental Distribution, and Crystal Structure
Crystals 2021, 11, x FOR PEER REVIEW 6 of 15 molten mixture, the maximum Na + to Ag + ion exchange percentage can exceed 80% while Na + to Li + ion exchange percentage remains less than 10% in 80% LiNO3 in LiNO3/NaNO3 molten mixture [1].  where β″-alumina, tetragonal and monoclinic phases of zirconia were observed. Identification of β″-alumina structure usually can be characterized by a few single peaks and a set of low scattered peaks with relatively low intensity at 35°-45°. The samples were very strong and no cracks were observed. Note in the samples before and after ion exchange, both tetragonal and monoclinic zirconia were observed. This is not surprising since 3YSZ is not a fully stabilized zirconia. It is known that tetragonal zirconia can slowly transforms to monoclinic zirconia (sometimes referred to as t-m transformation) over a rather narrow but important temperature range, typically room temperature to around 400 °C over extended period, which is referred to as low-temperature degradation (LTD) [22]. This phenomenon had been an issue in biomedical applications, such as hip implants and dental restorations, before the LTD mechanism was discovered. It is obvious t-m transformation has occurred after ion exchange process based on the suppressed intensity of tetragonal phase and increasing intensity of monoclinic phase for a few major peaks (indicated by double arrows).   3 where β"-alumina, tetragonal and monoclinic phases of zirconia were observed. Identification of β"-alumina structure usually can be characterized by a few single peaks and a set of low scattered peaks with relatively low intensity at 35 • -45 • . The samples were very strong and no cracks were observed. Note in the samples before and after ion exchange, both tetragonal and monoclinic zirconia were observed. This is not surprising since 3YSZ is not a fully stabilized zirconia. It is known that tetragonal zirconia can slowly transforms to monoclinic zirconia (sometimes referred to as t-m transformation) over a rather narrow but important temperature range, typically room temperature to around 400 • C over extended period, which is referred to as low-temperature degradation (LTD) [22]. This phenomenon had been an issue in biomedical applications, such as hip implants and dental restorations, before the LTD mechanism was discovered. It is obvious t-m transformation has occurred after ion exchange process based on the suppressed intensity of tetragonal phase and increasing intensity of monoclinic phase for a few major peaks (indicated by double arrows).  Figure 5 shows the extent of ion exchange as a function of time. A sample of Na-β″alumina + YSZ was ion exchanged in AgNO3 at 365 °C for up to 20 h. Subsequently, the sample was reverse ion exchanged in NaNO3 for an additional 61 h. The figure shows an increase in Ag + /[Ag + + Na + ] ratio eventually reaching saturation. One sample was further ion-exchanged for up to 60 h with no change in the Ag + /[Ag + + Na + ] ratio indicating saturation occurred in 20 h. After ion exchange in NaNO3, the Ag + /[Ag + + Na + ] decreased and eventually attained a lower saturation limit. Table 1 gives the weights of the sample after successive ion exchange. The 'before' column lists weight of the sample before subsequent ion exchange. The 'after' column lists weight after that ion exchange step. As seen in the table, during ion exchange in AgNO3, the weight increases since Ag has higher atomic mass than Na. For the same reason, when ion exchanged in NaNO3, the weight decreases, as expected. The angled arrows show weights after removing gold electrode/platinum grid from EIS measurements. There is virtually no change, indicating that there was no physical or chemical bonding between the electrodes and the sample. Table 2 shows similar data for ion exchange in LiNO3 and reverse ion exchange in NaNO3. In this case, weight decreases with increasing Li + /[Li + + Na + ] since lithium has a smaller atomic mass than sodium.  Figure 5 shows the extent of ion exchange as a function of time. A sample of Naβ"-alumina + YSZ was ion exchanged in AgNO 3 at 365 • C for up to 20 h. Subsequently, the sample was reverse ion exchanged in NaNO 3 for an additional 61 h. The figure shows an increase in Ag + /[Ag + + Na + ] ratio eventually reaching saturation. One sample was further ion-exchanged for up to 60 h with no change in the Ag + /[Ag + + Na + ] ratio indicating saturation occurred in 20 h. After ion exchange in NaNO 3 , the Ag + /[Ag + + Na + ] decreased and eventually attained a lower saturation limit. Table 1 gives the weights of the sample after successive ion exchange. The 'before' column lists weight of the sample before subsequent ion exchange. The 'after' column lists weight after that ion exchange step. As seen in the table, during ion exchange in AgNO 3 , the weight increases since Ag has higher atomic mass than Na. For the same reason, when ion exchanged in NaNO 3 , the weight decreases, as expected. The angled arrows show weights after removing gold electrode/platinum grid from EIS measurements. There is virtually no change, indicating that there was no physical or chemical bonding between the electrodes and the sample. Table 2 shows similar data for ion exchange in LiNO 3 and reverse ion exchange in NaNO 3 . In this case, weight decreases with increasing Li + /[Li + + Na + ] since lithium has a smaller atomic mass than sodium.  Note: Each change of arrow direction from an upper row to a lower row corresponds to an EIS measurement and gentle removal of Au electrode.     Figure 6 shows the ionic conductivity measured by EIS on a fully converted sample and after ion exchange for 24 h in LiNO3 at 300 °C. Representative EIS spectra are shown in Figure 6a,b. The spectra show no semicircles which are usually seen in electrochemical cells such as in fuel cells with active electrodes. This is partly due to poor electrode performance at low temperatures with pure Au electrodes. On the other hand, wire inductance can play a role too so that semicircles can be completely overlapped by inductance, the true semicircle in this case may be recovered by firstly measuring wire/metal-contact EIS spectrum and followed by subtracting wire/metal-contact spectrum point by point from measured wire/metal-contact + sample EIS spectrum [23]. Removal of the inductance is particularly important if separation of grain and grain boundary resistance is required. Similar behavior has been noted for some other solid state lithium ion conductors [23]. Since in this study, total ionic conductivity is of most interest, we therefore directly take the intercept in the high frequency range with real axis for the conductivity measurement. Figure 6c shows the Arrhenius plots of the total ionic conductivity. Both samples exhibit an Arrhenius behavior. The activation energy for the converted sample is 0.13 eV while it is 0.18 eV for the ion exchanged sample. These two values agrees relatively well with that of reported activation energies of single crystal β″-alumina of 0.10-0.33 eV and polycrystalline β″-alumina of 0.16-0.22 eV [1].The room temperature conductivities were estimated by extrapolation. The estimated total ionic conductivities at room temperature are 3.6 × 10 −3 S cm −1 and 7.5 × 10 −4 S cm −1 for the as-converted and ion-exchanged samples, respectively. Koh et al. reported vapor phase exchange of Li + to replace Na + [18]. The extrapolated conductivity at room temperature in their work was ~7 × 10 −5 S cm −1 . The conductivity of the Li-ion exchanged sample likely contains contributions from both Na + and Li + ions. However, it has been reported that the Li + transport number is nearly one if the Li + /(Na + + Li + ) ratio is greater than about 0.5 in Li + /Na + -β-alumina [17]. Since β and β″ have similar structures, we expect the partially ion-exchanged Li-β″-alumina to also be a predominantly Li + -ion conductor if Li + /(Na + + Li + ) ratio is greater than 0.5 in Li + /Na + -β″-alumina. In Figure 4, Li + /(Na + + Li + ) ratio is about 0.35, the composite is a mixed Na + and Li + conductor with Li + being the dominant conducting species, this may partially contribute to the measured higher conductivity in the ion exchanged Li + /Na + -β-alumina than the extrapolated conductivity from Koh et al.'s work.

Conductivity of as Converted and Ion-Exchanged Samples
Note: Each change of arrow direction from an upper row to a lower row corresponds to an EIS measurement and gentle removal of Au electrode. Figure 6 shows the ionic conductivity measured by EIS on a fully converted sample and after ion exchange for 24 h in LiNO 3 at 300 • C. Representative EIS spectra are shown in Figure 6a,b. The spectra show no semicircles which are usually seen in electrochemical cells such as in fuel cells with active electrodes. This is partly due to poor electrode performance at low temperatures with pure Au electrodes. On the other hand, wire inductance can play a role too so that semicircles can be completely overlapped by inductance, the true semicircle in this case may be recovered by firstly measuring wire/metal-contact EIS spectrum and followed by subtracting wire/metal-contact spectrum point by point from measured wire/metal-contact + sample EIS spectrum [23]. Removal of the inductance is particularly important if separation of grain and grain boundary resistance is required. Similar behavior has been noted for some other solid state lithium ion conductors [23]. Since in this study, total ionic conductivity is of most interest, we therefore directly take the intercept in the high frequency range with real axis for the conductivity measurement. Figure 6c shows the Arrhenius plots of the total ionic conductivity. Both samples exhibit an Arrhenius behavior. The activation energy for the converted sample is 0.13 eV while it is 0.18 eV for the ion exchanged sample. These two values agrees relatively well with that of reported activation energies of single crystal β"-alumina of 0.10-0.33 eV and polycrystalline β"-alumina of 0.16-0.22 eV [1].The room temperature conductivities were estimated by extrapolation. The estimated total ionic conductivities at room temperature are 3.6 × 10 −3 S cm −1 and 7.5 × 10 −4 S cm −1 for the as-converted and ion-exchanged samples, respectively. Koh et al. reported vapor phase exchange of Li + to replace Na + [18]. The extrapolated conductivity at room temperature in their work was~7 × 10 −5 S cm −1 . The conductivity of the Li-ion exchanged sample likely contains contributions from both Na + and Li + ions. However, it has been reported that the Li + transport number is nearly one if the Li + /(Na + + Li + ) ratio is greater than about 0.5 in Li + /Na + -β-alumina [17]. Since β and β" have similar structures, we expect the partially ion-exchanged Li-β"-alumina to also be a predominantly Li + -ion conductor if Li + /(Na + + Li + ) ratio is greater than 0.5 in Li + /Na + -β"-alumina. In Figure 4, Li + /(Na + + Li + ) ratio is about 0.35, the composite is a mixed Na + and Li + conductor with Li + being the dominant conducting species, this may partially contribute to the measured higher conductivity in the ion exchanged Li + /Na + -β-alumina than the extrapolated conductivity from Koh et al.'s work.  EIS spectra for a). and intercept with real axis is taken as the total ionic conductivity; (c) Arrhenius plots of the measured conductivity on a fully converted sample and after ion exchange in LiNO3 for 24 h at 300 °C. Figure 7 shows Arrhenius plots of the ionic conductivity of the as-converted Na-β″alumina + YSZ sample, after ion exchange in molten LiNO3, and after reverse exchange in NaNO3 as a function of temperature and time for two samples. The conductivity is the highest for the as converted Na-β″-alumina + YSZ, and the lowest after ion exchanged in LiNO3 and reversely ion exchanged in NaNO3. The conductivity is slightly higher in the as-converted Na-β″-alumina + YSZ sample at 1350 °C indicating slightly higher Na + concentration, but becomes slightly lower after LiNO3 ion exchange and NaNO3 reverse ion exchange in the same sample. Since we have seen a dramatic reduction of conductivity after LiNO3 ion exchange, a sample containing higher initial Na + concentration will likely have higher Li+ concentration after reaching Li + saturation. Upon reverse ion exchange, a higher Na + concentration may be replaced by a higher Li + concentration resulting a lower overall conductivity. Figure 6. Ionic conductivity measured by EIS on a fully converted sample and after ion exchange for 24 h in LiNO 3 at 300 • C. (a) EIS spectra for a fully converted sample (EIS measured at 381 • C) and after ion exchange for 24 h in LiNO 3 at 300 • C (EIS measured at 387 • C). (b) Enlarged EIS spectra for a). and intercept with real axis is taken as the total ionic conductivity; (c) Arrhenius plots of the measured conductivity on a fully converted sample and after ion exchange in LiNO 3 for 24 h at 300 • C. Figure 7 shows Arrhenius plots of the ionic conductivity of the as-converted Na-β"alumina + YSZ sample, after ion exchange in molten LiNO 3 , and after reverse exchange in NaNO 3 as a function of temperature and time for two samples. The conductivity is the highest for the as converted Na-β"-alumina + YSZ, and the lowest after ion exchanged in LiNO 3 and reversely ion exchanged in NaNO 3 . The conductivity is slightly higher in the as-converted Na-β"-alumina + YSZ sample at 1350 • C indicating slightly higher Na + concentration, but becomes slightly lower after LiNO 3 ion exchange and NaNO 3 reverse ion exchange in the same sample. Since we have seen a dramatic reduction of conductivity after LiNO 3 ion exchange, a sample containing higher initial Na + concentration will likely have higher Li+ concentration after reaching Li + saturation. Upon reverse ion exchange, a higher Na + concentration may be replaced by a higher Li + concentration resulting a lower overall conductivity. Figure 8 shows Arrhenius plots of the ionic conductivity after silver ion exchange for various periods of time. As seen in the figure, the conductivity decreases with increased Ag + /[Ag + + Na + ] ratio and saturated in about 3 h. Reverse ion exchange by NaNO 3 did not recover the conductivity to the initial value in the as-converted state. Crystals 2021, 11, x FOR PEER REVIEW 11 of 15 Figure 7. Arrhenius plots of the measured conductivity of the as fabricated samples and after successive lithium ion exchange and after reverse exchange in NaNO3. Figure 8 shows Arrhenius plots of the ionic conductivity after silver ion exchange for various periods of time. As seen in the figure, the conductivity decreases with increased Ag + /[Ag + + Na + ] ratio and saturated in about 3 h. Reverse ion exchange by NaNO3 did not recover the conductivity to the initial value in the as-converted state.

Stability of Ag-β″-Alumina + YSZ Composites
Samples of Ag-β″-alumina + YSZ were heated in air at 900 °C for various periods of time (up to 20 h) and their weights were measured. The initial mass of one sample was 1.1797 g. After 3 h, the mass of the sample was 1.1784 g. The surface of the sample was metallic indicating some loss of oxygen and formation of Ag metal. Figure 9a shows a photograph of the sample before heat treatment. Figure 9b shows a photograph of the sample after the heat treatment. The loss of mass attributed to oxygen corresponds to 0.0013 g and the corresponding moles of oxygen lost was 8.13 × 10 −5 mol. The sample was then etched in nitric acid to dissolve silver from the surface. The weight of the sample after leaching was 1.1665 g. This corresponds to a loss of silver of 0.0119 g. The corresponding moles of silver lost was 1.1 × 10 −4 moles. Thus, the mole ratio of loss corresponds to Ag1.35O. Ideally, it should be Ag2O. Given the very small mass loss, especially of oxygen, the accuracy of the balance is not sufficient. So we will assume that the loss of mass of the two elements must be in 2(Ag) to 1(O) ratio. The vapor phase process for the conversion of -Al2O3 + YSZ is made possible because Na-β″-alumina is a sodium ion conductor and YSZ is an oxygen ion conductor. This allows the conversion by incorporation of Na2O as a coupled transport of Na + through the formed Na-β″-alumina and of O 2− through YSZ. Detailed mechanism of the process has been described by Parthasarathy and Virkar [16].

Stability of Ag-β"-Alumina + YSZ Composites
Samples of Ag-β"-alumina + YSZ were heated in air at 900 • C for various periods of time (up to 20 h) and their weights were measured. The initial mass of one sample was 1.1797 g. After 3 h, the mass of the sample was 1.1784 g. The surface of the sample was metallic indicating some loss of oxygen and formation of Ag metal. Figure 9a shows a photograph of the sample before heat treatment. Figure 9b shows a photograph of the sample after the heat treatment. The loss of mass attributed to oxygen corresponds to 0.0013 g and the corresponding moles of oxygen lost was 8.13 × 10 −5 mol. The sample was then etched in nitric acid to dissolve silver from the surface. The weight of the sample after leaching was 1.1665 g. This corresponds to a loss of silver of 0.0119 g. The corresponding moles of silver lost was 1.1 × 10 −4 moles. Thus, the mole ratio of loss corresponds to Ag 1.35 O. Ideally, it should be Ag 2 O. Given the very small mass loss, especially of oxygen, the accuracy of the balance is not sufficient. So we will assume that the loss of mass of the two elements must be in 2(Ag) to 1(O) ratio. The vapor phase process for the conversion of -Al2O3 + YSZ is made possible because Na-β″-alumina is a sodium ion conductor and YSZ is an oxygen ion conductor. This allows the conversion by incorporation of Na2O as a coupled transport of Na + through the formed Na-β″-alumina and of O 2− through YSZ. Detailed mechanism of the process has been described by Parthasarathy and Virkar [16]. The process occurs because reaction (1) is thermodynamically favored. The formation of Ag-β″-alumina + YSZ by ion exchange in molten AgNO3 starting with Na-β″-alumina + YSZ is thermodynamically favored since it is only a reaction involving entropy change with essentially no enthalpy change. This makes it possible to make many β″-alumina capable of transporting other cations by ion exchange, even though such phases may not The vapor phase process for the conversion of α-Al 2 O 3 + YSZ is made possible because Na-β"-alumina is a sodium ion conductor and YSZ is an oxygen ion conductor. This allows the conversion by incorporation of Na 2 O as a coupled transport of Na + through the formed Na-β"-alumina and of O 2− through YSZ. Detailed mechanism of the process has been described by Parthasarathy and Virkar [16].
The process occurs because reaction (1) is thermodynamically favored. The formation of Ag-β"-alumina + YSZ by ion exchange in molten AgNO 3 starting with Na-β"-alumina + YSZ is thermodynamically favored since it is only a reaction involving entropy change with essentially no enthalpy change. This makes it possible to make many β"-alumina capable of transporting other cations by ion exchange, even though such phases may not be thermodynamically stable. Since the alumina spinel blocks in β"-alumina and YSZ are very refractory materials, such phases are kinetically stable.
When heated to a high temperature, e.g., 900 • C, there is sufficient conductivity for oxygen ions in YSZ so that, what makes possible to make the original Na-β"-alumina + YSZ by coupled transport, also makes the thermodynamically unstable Ag-β"-alumina to decompose. In this process some of Ag + is removed from Ag-β"-alumina and some of O 2− is removed from YSZ. The β"-alumina structure as such does not decompose since oxygen ion diffusion in the spinel block is very sluggish. While the kinetics of the decomposition process is believed to be controlled by coupled diffusion of 2Ag + through Ag-β"-alumina and O 2− through YSZ. However, it is possible to remove oxygen from YSZ. So the process involves some removal of Ag + from Ag-β"-alumina and some removal of O 2− from YSZ. If this happens, it is conceivable the there may be some positive charge in YSZ grains and balancing negative charge in Ag-β"-alumina, which may be similar to that of space charge phenomenon along grain boundaries of sintered polycrystalline yttrium stabilized zirconia [24]. Alternatively, some electronic transport may occur through both Ag-β"-alumina and YSZ to remove Ag and O by the reactions: and: (6) and the 2e are transferred to Ag + at the surface. Otherwise, O 2 and Ag may form inside the sample. Since Ag was observed only at the surface, it means the charge transfer should mainly have started from Ag-β"-alumina/YSZ grain boundary at the surface.
In such a case, Ag-β"-alumina becomes slightly silver-deficient and YSZ becomes slightly oxygen deficient. Figure 10a shows a fractured sample which has turned dark in color in the interior and the surface is metallic. Figure 10b shows the sample after etching.
decompose. In this process some of Ag + is removed from Ag-β″-alumina and some of O 2− is removed from YSZ. The β″-alumina structure as such does not decompose since oxygen ion diffusion in the spinel block is very sluggish. While the kinetics of the decomposition process is believed to be controlled by coupled diffusion of 2Ag + through Ag-β″-alumina and O 2− through YSZ. However, it is possible to remove oxygen from YSZ. So the process involves some removal of Ag + from Ag-β″-alumina and some removal of O 2− from YSZ. If this happens, it is conceivable the there may be some positive charge in YSZ grains and balancing negative charge in Ag-β″-alumina, which may be similar to that of space charge phenomenon along grain boundaries of sintered polycrystalline yttrium stabilized zirconia [24]. Alternatively, some electronic transport may occur through both Ag-β″-alumina and YSZ to remove Ag and O by the reactions: 2Ag + + 2e  2Ag (5) and: O 2- 1 /2O2 (g) + 2e (6) and the 2e are transferred to Ag + at the surface. Otherwise, O2 and Ag may form inside the sample. Since Ag was observed only at the surface, it means the charge transfer should mainly have started from Ag-β″-alumina/YSZ grain boundary at the surface.
In such a case, Ag-β″-alumina becomes slightly silver-deficient and YSZ becomes slightly oxygen deficient. Figure 10a shows a fractured sample which has turned dark in color in the interior and the surface is metallic. Figure 10b shows the sample after etching.

Conclusions
Na-β″-alumina + YSZ two phase composite solid electrolytes were fabricated by vapor phase conversion of sintered -alumina + YSZ composites. Na-β″-alumina + YSZ composites were ion-exchanged in AgNO3 and LiNO3 for various periods of time to respectively form Ag-β″-alumina + YSZ and Li-β″-alumina + YSZ composites, which are respectively silver and lithium ion conductors. Their conductivity was measured by electrochemical impedance spectroscopy (EIS), also as a function of the degree of ion exchange. EDS analysis was performed on the ion-exchanged samples to further confirm the occurrence of ion exchange. When Ag-β″-alumina + YSZ samples were heated to 900 °C

Conclusions
Na-β"-alumina + YSZ two phase composite solid electrolytes were fabricated by vapor phase conversion of sintered α-alumina + YSZ composites. Na-β"-alumina + YSZ composites were ion-exchanged in AgNO 3 and LiNO 3 for various periods of time to respectively form Ag-β"-alumina + YSZ and Li-β"-alumina + YSZ composites, which are respectively silver and lithium ion conductors. Their conductivity was measured by electrochemical impedance spectroscopy (EIS), also as a function of the degree of ion exchange. EDS analysis was performed on the ion-exchanged samples to further confirm the occurrence of ion exchange. When Ag-β"-alumina + YSZ samples were heated to 900 • C in air, a thin layer of metallic silver formed on the surface. This was attributed to the thermodynamic instability of Ag-β"-alumina/YSZ composite The kinetics of the decomposition process is believed to be controlled by coupled diffusion of 2Ag + through Ag-β"-alumina and O 2− through YSZ.