Chemically Driven Ion Exchanging Synthesis of Na5YSi4O12-Based Glass-Ceramic Proton Conductors

We have developed 12-membered silica-tetrahedra-ringed Na5YSi4O12-type sodium ion conducting glass-ceramics on the basis of the composition Na3+3x-yR1-xPySi3-yO9 (R: rare earth elements; denoted as Narpsio); especially, the material of Na4Y0.6P0.2Si2.8O9 with the combined parameters of (x, y) = (0.4, 0.2) gives rise to the maximum conductivity of 1 × 10−1 Scm−1 at 300 °C. Because glass-ceramics generally have the advantage of structural rigidity and chemical durability over sintered polycrystalline ceramics, the present study employed glass-ceramic Narpsio to perform chemically driven ion exchange of Na+ with protonated water molecules with an aim to produce a proton conductor. The ion exchange was carried out in a hydrochloric acid solution by changing immersion time, temperature, and acid concentration. The ion exchanged Na4Y0.6P0.2Si2.8O9-based glass-ceramics were analyzed by the complex impedance method, and the proton conductivity was found to exhibit 3 × 10−4 Scm−1 at 300 °C with the activation energy of 59 kJ/mol. The dependence of humidity-sensitive conductivity of the ion exchanged bulk glass-ceramics was also examined; the conductivity increased almost linearly from 0.6 × 10−4 Scm−1 in dry air to 1.5 × 10−4 Scm−1 in 75% humid ambience at 300 °C. Thus, the ion exchanged glass-ceramics can be considered to be high temperature proton conductors as well as humidity sensors.


Introduction
Considering the exchanging feasibility of the charge-carriers with a different kind of ions in a solid electrolyte, some chemical methods have been studied for a long time in order to realize another kind of ion conductor. Using the first-generation ceramic sodium ion conductor of Na-β/β"-alumina (e.g., β: NaAl 11 O 17 and β": NaAl 5 O 8 ), hydronium β/β"-alumina was obtained by acidic treatment of ceramic Na/K/-β/β"-alumina in order to avoid cracking during ion-exchange of Na + and K + ions with H 3 O + in H 2 SO 4 solution [1,2]. The second-generation conductor of NASICON (Na 1+x Zr 2 P 3−x Si x O 12 ) was confirmed to thoroughly convert to proton conductors by ion exchange in acid, alkaline aqueous solution and even in water [3][4][5]. Currently NASICON-type Li 1+x Ti 2 P 3-x Si x O 12 and Na 1+x Ti 2 P 3-x Si x O 12 solid electrolytes were also demonstrated to perform ion exchange with hydronium ions [6,7]. In the third generation Na 5 RSi 4 O 12 (R: rare-earth elements)-type sodium ion conductors [8,9], we employed the unprecedented field-assisted ion exchange method which applied dc voltage to a solid specimen at an elevated temperature of several tens in • C to release the induced strain during the process [10]. However, because of micro cracking during ion exchange of bulk specimens, no practically satisfactory bulk ion conductor has yet been produced by the ion exchange method for applications, such as solid electrolytes and sensors.
Our present aim is to produce bulk ceramic protonic conductors by ion exchange. Most of the abovementioned materials were polycrystalline ceramics or their powders. As glass-ceramics generally have structural rigidity against aqueous chemicals, we employed Na + ion conductive glass-ceramics of Na 5 RSi 4 O 12 (R: rare earth elements)-type sodium rare-earth silicophosphates in the system Na 2 O-R 2 O 3 -P 2 O 5 -SiO 2 , which will be abbreviated as Narpsio in the following [8,11]. We originally developed Na 5 YSi 4 O 12 -type Narpsio conductors on the basis of the composition Na 3+3x-y Y 1-x P y Si 3-y O 9 with appropriate parameters of x and y. Because Na + ion glass-ceramics can be synthesized with the various combination of the composition parameters x and y, the use of Narpsio has an advantage to develop suitable materials for practical devices.
The Na 5 YSi 4 O 12 structure consists of tunneling channels of Na + ions surrounded by 12-membered rings of SiO 4 tetrahedra along the c-axis, forming conduction paths. A unit cell contains 14 mobile (15%) and 76 bonding (85%) Na + ions. Narpsio materials were also found to be appropriate for the production of glass-ceramics without phase separation during crystallization from original glasses [11][12][13][14][15][16][17][18][19][20]. We currently found that those glassceramics can incorporate K + , two times larger than Na + in volume, to some extent [21]. Considering the ion-exchanging capability, the present study focused on the fundamental glass-ceramic Narpsio of Na 4 Y 0.6 P 0.2 Si 2.8 O 9 under (x, y) = (0.4, 0.2) which gives rise to the maximum conductivity of 1 × 10 −1 Scm −1 at 300 • C [9,[11][12][13][14] as the target material for conversion of sodium to hydronium ion conductors by chemical treatment in acid solutions. Narpsio glass-ceramics have another advantage of improved grain boundaries conduction due to the matrix-forming amorphous structure [11][12][13][14][15][16][17][18][19][20] because exuding Na + ions in grains exchange with permeating H 3 O + through grain boundaries. We firstly conducted ion exchange experiments using Narpsio powders to find the optimum conditions of the processing time, temperature, and solution concentration, then performed the production of protonic conducting bulk glass-ceramics under the appropriate conditions.

Materials Preparation
The starting powders were synthesized from the reagents of anhydrous Na 2 CO 3 (99.8% pure, Wako, Japan), Y 2 O 3 (99.99% pure, Wako, Japan), NH 4 H 2 PO 4 (99.0% pure, Wako, Japan), and SiO 2 (99.9% pure, Wako, Japan). Those powders were weighed according to the composition of Na 4 Y 0.6 P 0.2 Si 2.8 O 9 , thereafter mixed by ball-milling. The mixture was calcined at the temperatures of 400 • C and 900 • C for 0.5 h to evacuate NH 3 and CO 2 , respectively. The calcined powders were heated up to 1350 • C and melted in a Pt crucible for 1 h in air, then rapidly poured into cylindrical carbon dice to form glass. After annealing at 500 • C for 6h for nucleation, the annealed glass specimens were crystallized at 900 • C for 5 h according to the previous reports ( Figure 1a) [11][12][13][14][15][16]. The relative densities of crystallized bulk specimens were evaluated by the Archimedes method in comparison with theoretical values, which were determined by pycnometry.

Ion Exchange Procedure
The abovementioned ion exchange of polycrystalline Na/K β/β"-Al 2 O 3 was carried out by soaking in hot H 2 SO 4 . However, we employed dilute hydrochloric acid as the exchanging medium for gradual exchange. To evaluate the conditions for ion exchange, such as concentration of HCl aqueous solution and immersion period of solids, ball-milled and screened powders of glass-ceramics with a size of 46-105 µm in diameter were first subjected to ion exchange experiments (Figure 1a,b); the powders of 1 g were immersed in 50-166 mL HCl solution with various concentrations of 0.01 to 1.0 mol L −1 for 30 d (Figure 1a,b). The samples before and after ion exchange were named YP and YP-H. The ion exchange rate was determined by monitoring the pH of the solution (Equations (1)-(3)). The temperature effect of ion exchange was also evaluated according to the same manner mentioned above.

Ion Exchange Procedure
The abovementioned ion exchange of polycrystalline Na/K β/β″-Al2O3 was carried out by soaking in hot H2SO4. However, we employed dilute hydrochloric acid as the exchanging medium for gradual exchange. To evaluate the conditions for ion exchange, such as concentration of HCl aqueous solution and immersion period of solids, ball-milled and screened powders of glass-ceramics with a size of 46-105 μm in diameter were first subjected to ion exchange experiments (Figure 1a,b); the powders of 1 g were immersed in 50-166 mL HCl solution with various concentrations of 0.01 to 1.0 mol L −1 for 30 d ( Figure  1a,b). The samples before and after ion exchange were named YP and YP-H. The ion exchange rate was determined by monitoring the pH of the solution (Equations (1)-(3)). The temperature effect of ion exchange was also evaluated according to the same manner mentioned above.

XRD, SEM, and Thermal Analyses of Glass and Glass-Ceramics
Identification of the crystalline phases was performed on the crushed powders of crystallized specimens by the X-ray diffraction (XRD; Rigaku MiniFlex II) method. The XRD measurements were calculated between 10 and 40° under the scanning speed of 3°･ min −1 . Scanning electron micrographic (SEM; JEOL JSM-6701F) observation was also performed on the bulk samples chemically etched with 3% HF solution to evaluate the microstructure. The conductive coatings were performed using sputtering of carbon. Differential scanning calorimetry (DSC) was carried out on the prepared samples to confirm the changes in thermodynamic parameters before and after ion exchange. The sample was [ where [ where V sample : volume of sample/g, and [Na + ] in 1g : mobile [Na + ] in 1 g of sample /mol g −1 .

XRD, SEM, and Thermal Analyses of Glass and Glass-Ceramics
Identification of the crystalline phases was performed on the crushed powders of crystallized specimens by the X-ray diffraction (XRD; Rigaku MiniFlex II) method. The XRD measurements were calculated between 10 and 40 • under the scanning speed of 3 • ·min −1 . Scanning electron micrographic (SEM; JEOL JSM-6701F) observation was also performed on the bulk samples chemically etched with 3% HF solution to evaluate the microstructure. The conductive coatings were performed using sputtering of carbon. Differential scanning calorimetry (DSC) was carried out on the prepared samples to confirm the changes in thermodynamic parameters before and after ion exchange. The sample was packed in an aluminum pan, covered with an aluminum lid, and measured using a Rigaku DSC_8230. Thermogravimetric-mass spectrometry (TG-MS) was performed to analyze the gaseous components desorbed from the sample. The sample was packed in an alumina pan and measured simultaneously using a thermogravimetric (Netzsch, TG209 F1 Libra)-mass spectrometer (Netzsch, QMS403 D Aëolos) under the conditions of the heating rate of 10 • C min −1 , the He gas flow rate of 20 mL min −1 , and the sampling span of 10 s.

Measurements of Conduction Properties
Electrochemical impedance measurements were undertaken by the alternate current (AC) two-probe method on cylindrical glass-ceramics with a diameter and thickness of 14 mm and 2 mm, respectively. Electrodes were formed by sputtering gold on the polished surfaces. The ionic conductivities were measured by impedance spectroscopy (Solartron Analytical 1260A Impedance Analyzer and 1296A Dielectric Interface system). The applied AC field was in the frequency range from 10 mHz to 32 MHz, with a voltage amplitude of 300 mV. The temperature dependence of the conductivity was measured similarly at several temperatures ranging from 100 • C to 300 • C.
Furthermore, the conductivity of H + conductive glass-ceramics was measured under water vapor atmosphere to evaluate the effect of relative humidity on H + conductivity. The schematic diagram of the measurement apparatus is shown in Figure 2. Water in an eggplant flask was heated with a mantle heater to generate steam. The water was bubbled using an air pump, and the generated steam was introduced into a non-inductive tubular electric furnace. By changing the temperature of the mantle heater, the relative humidity of the water vapor on the introduction side was changed, and the conductivity was measured. The relative humidity was calculated by Equation (4).
where ϕ: relative humidity/%, e: partial pressure of water vapor/hPa, t: temperature/ • C, and e s (t): saturated water vapor pressure/hPa. To calculate the saturated water vapor pressure, the Tetens equation shown in Equation (5) was used.

Characterization of Original Narpsio Glass-Ceramics
The original glass and crystallized glass-ceramic specimens are compared to demonstrate the dense bodies in Figure 3. As can be seen in the figure, the precursor bulk glasses were transparent without apparent pores. The crystallized glass-ceramics were more than 98% dense of the theoretical value, and the crystalline phase of glass-ceramic specimens was confirmed as Na5RSi4O12-type by XRD by comparison with the international standard diffraction pattern (ICDD No. 00-032-1204 for Na5YSi4O12). In order to calculate the amount of water vapor depending on the temperature of the mantle heater, the dew point of the generated water vapor was measured using the lowpressure cooling dew-point method. Figure 2 shows the macroscopic dew-point meter used. After the temperature of the mantle heater reached the set temperature, air was introduced from the pump to bubble the deionized water in the eggplant flask. The temperature inside the apparatus and the temperature of the generated steam were kept at the same level by holding the flask in this state for a sufficient period of time. The glass tube, which is the outlet port, was then immersed in water maintained at a temperature of 95 • C or higher, and the temperature of the water was gradually lowered. The temperature at which dew condensed inside the glass tube was taken as the dew point of the generated water vapor. The ionic conductivities in a steam atmosphere were measured using an Agilent Technologies 4294A-Precision-Impedance Analyzer, similar to the method described above. The applied AC field had a frequency range from 40 Hz to 100 MHz, with a voltage amplitude of 300 mV. The temperature dependence of the conductivity was measured similarly at several temperatures ranging from 100 • C to 300 • C.

Characterization of Original Narpsio Glass-Ceramics
The original glass and crystallized glass-ceramic specimens are compared to demonstrate the dense bodies in Figure 3. As can be seen in the figure, the precursor bulk glasses were transparent without apparent pores. The crystallized glass-ceramics were more than 98% dense of the theoretical value, and the crystalline phase of glass-ceramic specimens was confirmed as Na 5 RSi 4 O 12 -type by XRD by comparison with the international standard diffraction pattern (ICDD No. 00-032-1204 for Na 5 YSi 4 O 12 ).

Characterization of Original Narpsio Glass-Ceramics
The original glass and crystallized glass-ceramic specimens are compared to demonstrate the dense bodies in Figure 3. As can be seen in the figure, the precursor bulk glasses were transparent without apparent pores. The crystallized glass-ceramics were more than 98% dense of the theoretical value, and the crystalline phase of glass-ceramic specimens was confirmed as Na5RSi4O12-type by XRD by comparison with the international standard diffraction pattern (ICDD No. 00-032-1204 for Na5YSi4O12).

Ion Exchange of Narpsio Glass-Ceramics
XRD analysis showed that when Narpsio powders were immersed in an aqueous HCl solution for 30 d at room temperature, the original Na5RSi4O12-type structure was maintained in the HCl concentration range of 0.01 to 0.1 M, whereas the crystalline phase was destroyed to amorphous over 0.     Figure 4a denote the peaks assigned to the Na5RSi4O12-type structure, which are abbreviated as N5 for convenience.
The monitored pH change of the solution with immersion time indicates that the ion exchange proceeded more rapidly from pH = 2 to an alkaline region up to pH=10 via a two-step processes at a higher temperature without structural destruction (Figure 5a). Based on the result of Figure 5a, the ion exchange ratio was calculated using Equation (1). The monitored pH change of the solution with immersion time indicates that the ion exchange proceeded more rapidly from pH = 2 to an alkaline region up to pH = 10 via a two-step processes at a higher temperature without structural destruction (Figure 5a). Based on the result of Figure 5a, the ion exchange ratio was calculated using Equation (1). The evaluated result is shown in Figure 5b. It was also noted that the ion exchange was completed within a few minutes at the first step I, even at a low temperature of 2 • C (Figure 5b). Possibly the second step II was considered to give rise to a slight surface corrosion, because the surface morphology was seen to be roughened by scattered pores (Figure 4d,e).  Figure 4a denote the peaks assigned to the Na5RSi4O12-type structure, which are abbreviated as N5 for convenience.
The monitored pH change of the solution with immersion time indicates that the ion exchange proceeded more rapidly from pH = 2 to an alkaline region up to pH=10 via a two-step processes at a higher temperature without structural destruction (Figure 5a). Based on the result of Figure 5a, the ion exchange ratio was calculated using Equation (1). The evaluated result is shown in Figure 5b. It was also noted that the ion exchange was completed within a few minutes at the first step I, even at a low temperature of 2 °C (Figure 5b). Possibly the second step II was considered to give rise to a slight surface corrosion, because the surface morphology was seen to be roughened by scattered pores (Figure  4d,e).  The surfaces of bulk glass-ceramic specimens thus treated exhibited no considerable change after ion exchange by SEM observation (Figure 7a,b), and XRD analysis confirmed the no destruction of the Na5RSi4O12-type structure (Figure 8a-d). However, as the longer time treatment at 25 °C gave mechanical damage to specimens, the temperature of 60 °C was chosen for the preparation of hydronium bulk glass-ceramics. The surfaces of bulk glass-ceramic specimens thus treated exhibited no considerable change after ion exchange by SEM observation (Figure 7a,b), and XRD analysis confirmed the no destruction of the Na 5 RSi 4 O 12 -type structure (Figure 8a-d). However, as the longer time treatment at 25 • C gave mechanical damage to specimens, the temperature of 60 • C was chosen for the preparation of hydronium bulk glass-ceramics.
The surfaces of bulk glass-ceramic specimens thus treated exhibited no considerabl change after ion exchange by SEM observation (Figure 7a,b), and XRD analysis confirmed the no destruction of the Na5RSi4O12-type structure (Figure 8a-d). However, as the longe time treatment at 25 °C gave mechanical damage to specimens, the temperature of 60 °C was chosen for the preparation of hydronium bulk glass-ceramics.  Endothermic peaks on HCl-untreated specimens were observed at 64.1 and 91.9 °C, and the total weight loss was within 2%, while the peaks were detected at 133.3 and 312.6 °C in addition to 47.6 and 79.6 °C on ion-exchanged ones (Figure 9). All peaks observed below 100 °C were attributed to evaporation of adsorbed water on surfaces. However, the endothermic peaks at 133.3 and 312.6 °C on ion-exchanged specimens are deduced to the evaporation of ion exchanged hydrated water from the inner bulks. The amount of water loss as protons from the bulk specimen was evaluated as 0.794 mol per 1 mol of glassceramics by TG analysis, while the mobile Na + concentration was calculated as 0.622 mol per 1 mol of glass-ceramics by comparison of specimen's weight with chemical formula. The consistency of the two values with each other within the experimental error indicates the one-to-one exchange of Na + of a glass-ceramic with H + of HCl solution. Endothermic peaks on HCl-untreated specimens were observed at 64.1 and 91.9 • C, and the total weight loss was within 2%, while the peaks were detected at 133.3 and 312.6 • C in addition to 47.6 and 79.6 • C on ion-exchanged ones (Figure 9). All peaks observed below 100 • C were attributed to evaporation of adsorbed water on surfaces. However, the endothermic peaks at 133.3 and 312.6 • C on ion-exchanged specimens are deduced to the evaporation of ion exchanged hydrated water from the inner bulks. The amount of water loss as protons from the bulk specimen was evaluated as 0.794 mol per 1 mol of glass-ceramics by TG analysis, while the mobile Na + concentration was calculated as 0.622 mol per 1 mol of glass-ceramics by comparison of specimen's weight with chemical formula. The consistency of the two values with each other within the experimental error indicates the one-to-one exchange of Na + of a glass-ceramic with H + of HCl solution.
°C in addition to 47.6 and 79.6 °C on ion-exchanged ones ( Figure 9). All peaks observe below 100 °C were attributed to evaporation of adsorbed water on surfaces. However, th endothermic peaks at 133.3 and 312.6 °C on ion-exchanged specimens are deduced to th evaporation of ion exchanged hydrated water from the inner bulks. The amount of wate loss as protons from the bulk specimen was evaluated as 0.794 mol per 1 mol of glas ceramics by TG analysis, while the mobile Na + concentration was calculated as 0.622 mo per 1 mol of glass-ceramics by comparison of specimen's weight with chemical formul The consistency of the two values with each other within the experimental error indicate the one-to-one exchange of Na + of a glass-ceramic with H + of HCl solution. Figure 9. TG-MS and DSC curves measured on Narpsio bulk glass-ceramics before and after ion exchange.

Conduction Properties of Ion Exchanged Narpsio Glass-Ceramics
The measured complex impedances are shown as an Arrhenius plot, where a single semicircle was observed at each temperature (Figure 10a,b). The result indicates that the separation of grains and grain boundaries-conductions were inseparable, and then the measured conductivities (σ) corresponded to the total of the two microstructural elements. The value of σ at 300 • C was 3.8 × 10 −4 Scm −1 with the activation energy of 58.6 kJ mol −1 for the most conductive bulk specimen. There are two main types of proton transfer: Grotthuss type and Vehicle type. In the Grotthuss type, a proton becomes H 3 O + when it receives an electron supply from an unpaired electron in the presence of water and can move by hopping against an unpaired electron on a neighboring water molecule when there are enough neighboring water molecules. In this case, the proton conduction can be achieved with a low activation energy because it does not require much energy for translational motion. On the other hand, in the Vehicle type, protons are given unpaired electrons by water molecules to become H 3 O + , and then they form a group and perform translational motion to conduct protons. A large amount of activation energy is required for the translational motion [22]. The proton transfer in crystallized glass after carrier ion exchange is considered to be of the Vehicle type due to the high activation energy. Although the conductivity of glass-ceramics decreased in the order of 10 −2 Scm −1 by ion exchange of Na + with H 3 O + , the value of σ of ion exchanged glass-ceramics can still be anticipated to be on the level of practical applications with further efforts. Because the microstructure of glass-ceramics strongly depends upon annealing time and temperature of nucleation and crystal growth, we are investigating the effects of those parameters on improvement of conduction properties. the conductivity of glass-ceramics decreased in the order of 10 −2 S cm −1 by ion exchange of Na + with H3O + , the value of σ of ion exchanged glass-ceramics can still be anticipated to be on the level of practical applications with further efforts. Because the microstructure of glass-ceramics strongly depends upon annealing time and temperature of nucleation and crystal growth, we are investigating the effects of those parameters on improvement of conduction properties. Although the top value of σ of ion exchanged bulk specimens reached to ca. 3 × 10 −4 S cm −1 at 300 °C, the conductivities were usually a little scattered. This can be attributed to the difference in unstable concentration of incorporated protons among specimens. With the aim at clarification of water vapor effect on conductivity, we conducted the σ measurements under various controlled humidity at 300 °C. The value of σ increased from 0.6 × 10 −4 S cm −1 in dry air to 1.5 × 10 −4 S cm −1 under 75% humidity, indicating humiditysensitive conduction in bulk specimens ( Figure 11). As the conductivity of the bulk specimen varies almost linearly with humidity, the ion exchanged glass-ceramics can be Although the top value of σ of ion exchanged bulk specimens reached to ca. 3 × 10 −4 Scm −1 at 300 • C, the conductivities were usually a little scattered. This can be attributed to the difference in unstable concentration of incorporated protons among specimens. With the aim at clarification of water vapor effect on conductivity, we conducted the σ measurements under various controlled humidity at 300 • C. The value of σ increased from 0.6 × 10 −4 Scm −1 in dry air to 1.5 × 10 −4 Scm −1 under 75% humidity, indicating humidity-sensitive conduction in bulk specimens ( Figure 11). As the conductivity of the bulk specimen varies almost linearly with humidity, the ion exchanged glass-ceramics can be applicable to humidity sensors at an elevated temperature, such as 300 • C. As for the water resistance of the samples, there is concern about the possibility of elution of bonding Na + during charge carrier ion exchange or under high-humidity conditions, so it is required in the future to improve the water resistance by adding Al or Zr.
Materials 2023, 16, x FOR PEER REVIEW 10 of 11 applicable to humidity sensors at an elevated temperature, such as 300 °C. As for the water resistance of the samples, there is concern about the possibility of elution of bonding Na + during charge carrier ion exchange or under high-humidity conditions, so it is required in the future to improve the water resistance by adding Al or Zr. Figure 11. Humidity-sensitive conductivity measured on ion exchanged bulk glass-ceramics at 300 °C.

Conclusions
The present study focused on the fundamental Na5YSi4O12-type glass-ceramic Narpsio on the basis of the composition Na3+3x-yY1-xPySi3-yO9, of which Na4Y0.6P0.2Si2.8O9 with the combined parameters of (x, y) = (0.4, 0.2) as the target material for conversion of so- Figure 11. Humidity-sensitive conductivity measured on ion exchanged bulk glass-ceramics at 300 • C.

Conclusions
The present study focused on the fundamental Na 5 YSi 4 O 12 -type glass-ceramic Narpsio on the basis of the composition Na 3+3x-y Y 1-x P y Si 3-y O 9 , of which Na 4 Y 0.6 P 0.2 Si 2.8 O 9 with the combined parameters of (x, y) = (0.4, 0.2) as the target material for conversion of sodium to hydronium ion conductors by chemical treatment in acid solutions. Taking into account the structural rigidity and chemical durability of glass-ceramics, chemically driven ion exchange of Na + with protonated water molecules in Na 4 Y 0.6 P 0.2 Si 2.8 O 9 -based glassceramics was performed. The value of σ at 300 • C was 3.8 × 10 −4 Scm −1 with the activation energy of 58.6 kJ mol −1 for the most conductive bulk specimen. The ion exchanged bulk glass-ceramics showed humidity-sensitive conductivity; σ increased from 0.6 × 10 −4 Scm −1 in dry air to 1.5 × 10 −4 Scm −1 in 75% humid ambience at 300 • C. Although the conductivity of glass-ceramics decreased in the order of 10 −2 Scm −1 by ion exchange of Na + with H 3 O + , the value of σ of ion exchanged glass-ceramics still can be anticipated to be on the level of practical applications with further efforts. The ion exchange is a promising method to convert the charge carrying ions to the different ones because the finding of a novel conductor is unimaginably beyond our effort. The use of glass-ceramics is also noticeable because the fabrication of thinner bulk specimens can be realized through the glass making process, where melts are thinned during cooling. Considering those circumstances, we are conducting the research to optimize ion exchange conditions for glass-ceramic materials to improve the proton conductivity up to ca. 10 −2 Scm −1 for practical applications.