Simultaneous Hetero- and Isovalent Doping as the Strategy for Improving Transport Properties of Proton Conductors Based on BaLaInO4

This work focused on the novel electrochemical energy material with significantly improved electrical properties. The novel complex oxide Ba1.1La0.9In0.5Y0.5O3.95 with layered perovskite structure was obtained for the first time. It was proven that the simultaneous introduction of barium and yttrium ions in the structure of BaLaInO4 leads to the increase in the unit cell volume of up to 4% and water uptake by about three times. The increase in the proton conductivity values was both due to an increase in the proton concentration and their mobility. The sample Ba1.1La0.9In0.5Y0.5O3.95 was a nearly pure proton conductor below 400 °C. The co-doping strategy allowed us to increase the protonic conductivity values up to two orders of magnitude and it is the successful method for the design of novel protonic conductors based on the layered perovskites.

In general, the realization of proton transfer is provided by the dissociative water uptake from the gas phase into the crystal lattice of the solid oxide. However, the crystal structure features determine the sites of protons localization. For oxides like doped barium cerates and zirconates, the proton species localize in the oxygen vacancies that appear through the acceptor doping [54]: In such systems, the amount of protons is small and limited by the amount of dopant. The oxygen-deficient perovskites and brownmillerites have oxygen vacancies in the structure without doping up to 0.5 mol per perovskite ABO3 formula unit. This leads to a significant increase in the amount of water uptake compared with doped perovskites [54]: In the structure of layered perovskites AA′BO4 the alternation of salt layers [AO] and perovskite layers [A′BO3] provides the presence of interlayer space in the structure, which is suitable for the insertion of protonic species up to 3 mol theoretically: From the point of view of protonic conductivity, the layered perovskites based on BaLaInO4, SrLaInO4, BaNdInO4, and BaNdScO4 were investigated [21][22][23][24][25][26][27][28][29][30][31]. The possibility of acceptor (Ca 2+ /Sr 2+ /Ba 2+ → La 3+ /Nd 3+ ) and donor (Zr 4+ /Ti 4+ /Nb 5+ → In 3+ ) doping was proven. It was shown that a significant amount of protons (up to 1.5 mol) are achieved only for doped compositions, and the increase of dopant concentration leads to the increase in water uptake due to increase in the interlayer space [31]. In the other words, the amount of proton current carriers in the structure increases with an increasing acceptor or dopant content. However, it is well known that the value of protonic conductivity is determined not only by the amount of protonic species but by their mobility as well. The mobility of protons depends on the many factors, including the bond energy with nearest atoms, the possibility to use the migration pathways and the presence of other structural defects. The last factor plays a significant role not only for the classic doped perovskites, but also for the novel block-layer proton conductors. It was shown that the formation of proton-aggregating clusters can be obtained at a small enough amount of acceptor or donor dopant [26,27]: This means that increase in the acceptor/donor dopant concentration leads to the trapping of protons. Therefore, this way (increase in dopant concentration of M′A or M˙B) is not prospective for obtaining of block-layered materials with high values of proton conductivity. On the other hand, for layered perovskites, it is known that an increase in the water uptake occurs with an increase in the size of the salt block, and this can be achieved In such systems, the amount of protons is small and limited by the amount of dopant. The oxygen-deficient perovskites and brownmillerites have oxygen vacancies in the structure without doping up to 0.5 mol per perovskite ABO 3 formula unit. This leads to a significant increase in the amount of water uptake compared with doped perovskites [54]: In the structure of layered perovskites AA BO 4 the alternation of salt layers [AO] and perovskite layers [A BO 3 ] provides the presence of interlayer space in the structure, which is suitable for the insertion of protonic species up to 3 mol theoretically: From the point of view of protonic conductivity, the layered perovskites based on BaLaInO 4 , SrLaInO 4 , BaNdInO 4, and BaNdScO 4 were investigated [21][22][23][24][25][26][27][28][29][30][31]. The possibility of acceptor (Ca 2+ /Sr 2+ /Ba 2+ → La 3+ /Nd 3+ ) and donor (Zr 4+ /Ti 4+ /Nb 5+ → In 3+ ) doping was proven. It was shown that a significant amount of protons (up to 1.5 mol) are achieved only for doped compositions, and the increase of dopant concentration leads to the increase in water uptake due to increase in the interlayer space [31]. In the other words, the amount of proton current carriers in the structure increases with an increasing acceptor or dopant content. However, it is well known that the value of protonic conductivity is determined not only by the amount of protonic species but by their mobility as well. The mobility of protons depends on the many factors, including the bond energy with nearest atoms, the possibility to use the migration pathways and the presence of other structural defects. The last factor plays a significant role not only for the classic doped perovskites, but also for the novel block-layer proton conductors. It was shown that the formation of proton-aggregating clusters can be obtained at a small enough amount of acceptor or donor dopant [26,27]: This means that increase in the acceptor/donor dopant concentration leads to the trapping of protons. Therefore, this way (increase in dopant concentration of M A or M˙B) is not prospective for obtaining of block-layered materials with high values of proton conductivity. On the other hand, for layered perovskites, it is known that an increase in the water uptake occurs with an increase in the size of the salt block, and this can be achieved by isovalet doping with a larger ion. Therefore, the strategy of introducing two types of dopants can lead to a more significant increase in proton conductivity.
In this paper, a novel method of improving of proton conductors based on blocklayered perovskite BaLaInO 4 is proposed. The idea of creation of an "optimal" concentration of oxygen vacancies by introducing the acceptor dopant Ba 2+ → La 3+ while simultaneously increasing the interlayer space by the isovalent doping Y 3+ → In 3+ by ions with bigger ionic radii is realized. The composition of Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 was obtained for the first time. The possibility for water uptake and realization of fast protonic transport was revealed.
It can be said that the block-layered perovskites are one of the newest classes among proton-conducting solid oxides and require further investigation.

Materials and Methods
The composition of Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 was prepared by a solid-state method. The initial powders of BaCO 3 , La 2 O 3 , In 2 O 3 , Y 2 O 3 were dried and weighed using Sartorius balances. The reagents were milling in an agate mortar and then calcined at 800-1300 • C (step of 100 • C, time of calcined 24 h). Figure 2 provides the pictures of the powders of the initial materials and the obtained composition. Figure 3 represents the scheme indicating the workflow and analysis. by isovalet doping with a larger ion. Therefore, the strategy of introducing two types of dopants can lead to a more significant increase in proton conductivity. In this paper, a novel method of improving of proton conductors based on blocklayered perovskite BaLaInO4 is proposed. The idea of creation of an "optimal" concentration of oxygen vacancies by introducing the acceptor dopant Ba 2+ → La 3+ while simultaneously increasing the interlayer space by the isovalent doping Y 3+ → In 3+ by ions with bigger ionic radii is realized. The composition of Ba1.1La0.9In0.5Y0.5O3.95 was obtained for the first time. The possibility for water uptake and realization of fast protonic transport was revealed.
It can be said that the block-layered perovskites are one of the newest classes among proton-conducting solid oxides and require further investigation.

Materials and Methods
The composition of Ba1.1La0.9In0.5Y0.5O3.95 was prepared by a solid-state method. The initial powders of BaCO3, La2O3, In2O3, Y2O3 were dried and weighed using Sartorius balances. The reagents were milling in an agate mortar and then calcined at 800-1300 °C (step of 100 °C, time of calcined 24 h). Figure 2 provides the pictures of the powders of the initial materials and the obtained composition. Figure 3 represents the scheme indicating the workflow and analysis.  The monitoring of the phase purity of the samples was performed using a Bruker Advance D8 Cu Kα diffractometer with Cu Kα radiation in the range of 2θ = 10 − 80° with a step of 0.01° and at a scanning rate of 0.5°/min. The scanning electron microscope JEOL JSM-6390 LV (WD 8.1 mm, aperture size 30 μm, EHT 20 kV, system vacuum 1.68×10 −6 mbar) was used to determine the morphology and chemical composition of the samples.  by isovalet doping with a larger ion. Therefore, the strategy of introducing two types of dopants can lead to a more significant increase in proton conductivity. In this paper, a novel method of improving of proton conductors based on blocklayered perovskite BaLaInO4 is proposed. The idea of creation of an "optimal" concentration of oxygen vacancies by introducing the acceptor dopant Ba 2+ → La 3+ while simultaneously increasing the interlayer space by the isovalent doping Y 3+ → In 3+ by ions with bigger ionic radii is realized. The composition of Ba1.1La0.9In0.5Y0.5O3.95 was obtained for the first time. The possibility for water uptake and realization of fast protonic transport was revealed.
It can be said that the block-layered perovskites are one of the newest classes among proton-conducting solid oxides and require further investigation.

Materials and Methods
The composition of Ba1.1La0.9In0.5Y0.5O3.95 was prepared by a solid-state method. The initial powders of BaCO3, La2O3, In2O3, Y2O3 were dried and weighed using Sartorius balances. The reagents were milling in an agate mortar and then calcined at 800-1300 °C (step of 100 °C, time of calcined 24 h). Figure 2 provides the pictures of the powders of the initial materials and the obtained composition. Figure 3 represents the scheme indicating the workflow and analysis.  The monitoring of the phase purity of the samples was performed using a Bruker Advance D8 Cu Kα diffractometer with Cu Kα radiation in the range of 2θ = 10 − 80° with a step of 0.01° and at a scanning rate of 0.5°/min. The scanning electron microscope JEOL JSM-6390 LV (WD 8.1 mm, aperture size 30 μm, EHT 20 kV, system vacuum 1.68×10 −6 mbar) was used to determine the morphology and chemical composition of the samples. The monitoring of the phase purity of the samples was performed using a Bruker Advance D8 Cu K α diffractometer with Cu Kα radiation in the range of 2θ = 10 − 80 • with a step of 0.01 • and at a scanning rate of 0.5 • /min. The scanning electron microscope JEOL JSM-6390 LV (WD 8.1 mm, aperture size 30 µm, EHT 20 kV, system vacuum 1.68×10 −6 mbar) was used to determine the morphology and chemical composition of the samples.
Thermogravimetry (TG) and mass-spectrometry (MS) analysis were performed using the STA 409 PC Netzsch Analyser coupled with a QMS 403 C Aëolos mass spectrometer. The preliminarily hydrated samples were heated at the rate of 10 • C/min in a corundum crucible under a flow of dry Ar at the temperature range of 40-1100 • C. The hydrated forms of the samples were prepared by slow cooling (1 • C/min, 1100-150 • C) in wet Ar.
The impedance spectroscopy measurements were performed on the pressed cylindrical pellets (1300 • C, 24 h) using a Z-1000P (Elins, RF) impedance spectrometer. The measurements were carried out in the temperature range 200-1000 • C every 10-20 • C with a cooling rate of 1 • /min under dry and wet air or Ar. Dry gas was obtained by the circulation through P 2 O 5 (pH 2 O = 3.5 × 10 −5 atm). Wet gas was produced by bubbling first through distilled water and then through saturated solution of KBr (pH 2 O = 2×10 −2 atm). The conductivity was also measured at different partial oxygen pressures pO 2 for some temperatures. The pO 2 was controlled by electrochemical method. The oxygen pump (and sensor) from Y-stabilized ZrO 2 ceramic was used to control (and measure) pO 2 . Before the measurements, the samples were equilibrated up to constant values of resistance for 3-5 h.

X-ray, SEM and TG Characterization
The phase composition of the obtained sample Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 was checked via scanning electron microscopy (SEM) coupled with energy dispersive analysis (EDS). Figure 4 shows the morphology of the powder sample. The grains of co-doped sample are round-shaped (~3-5 µm) and form the agglomerates of 10-20 µm with an irregular shape. An element analysis was performed at the polished cleavages of the ceramic samples via the EDS method. The experimental content of the elements was in good agreement with the theoretical values (Table 1). Thermogravimetry (TG) and mass-spectrometry (MS) analysis were performed using the STA 409 PC Netzsch Analyser coupled with a QMS 403 C Aëolos mass spectrometer. The preliminarily hydrated samples were heated at the rate of 10 °C/min in a corundum crucible under a flow of dry Ar at the temperature range of 40-1100 °C. The hydrated forms of the samples were prepared by slow cooling (1 °C/min, 1100-150 °C) in wet Ar.
The impedance spectroscopy measurements were performed on the pressed cylindrical pellets (1300 °C, 24 h) using a Z-1000P (Elins, RF) impedance spectrometer. The measurements were carried out in the temperature range 200-1000 °C every 10-20 °C with a cooling rate of 1°/min under dry and wet air or Ar. Dry gas was obtained by the circulation through P2O5 (pH2O = 3.5 × 10 −5 atm). Wet gas was produced by bubbling first through distilled water and then through saturated solution of KBr (pH2O = 2×10 −2 atm). The conductivity was also measured at different partial oxygen pressures pO2 for some temperatures. The pO2 was controlled by electrochemical method. The oxygen pump (and sensor) from Y-stabilized ZrO2 ceramic was used to control (and measure) pO2. Before the measurements, the samples were equilibrated up to constant values of resistance for 3-5 h.

X-ray, SEM and TG Characterization
The phase composition of the obtained sample Ba1.1La0.9In0.5Y0.5O3.95 was checked via scanning electron microscopy (SEM) coupled with energy dispersive analysis (EDS).  (Table 1).    The XRD pattern of the co-doped sample Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 is shown in Figure 5. (Figure 5a). It is observed that all reflexes belong to the phase with orthorhombic symmetry, so the sample exhibits an RP-structure with the Pbca space group in agreement with the XRD Materials 2021, 14, 6240 5 of 12 data for the parent phase BaLaInO 4 [24]. The cell parameters for undoped BaLaInO 4 [24] and doped Ba 1.1 La 0.9 InO 3.95 [24], Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 samples are shown in Table 2.
As it was shown earlier, the acceptor doping of lanthanum sublattice Ba 2+ → La 3+ led to an increase in all unit cell parameters and the unit cell volume. The simultaneous doping Ba 2+ → La 3+ and Y 3+ → In 3+ leads to the same effect, but the increase in the unit cell volume during co-doping is bigger (~4%) compared with increase in the case of only acceptor doping (~1%). It should be noted that the compositions with a yttrium content over 50% were not singe phases (Figure 5b, line 4). After measuring the conductivity of the synthesized phase Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 as a function of pO 2 at different temperatures and high humidity, X-ray powder diffraction patterns of the pellets were obtained (Figure 5b. line 3). Decomposition, due to the highly reduced atmosphere or to the high humidity to which the materials were exposed, did not take place. The XRD pattern of the co-doped sample Ba1.1La0.9In0.5Y0.5O3.95 is shown in Figure 5. (Figure 5a). It is observed that all reflexes belong to the phase with orthorhombic symmetry, so the sample exhibits an RP-structure with the Pbca space group in agreement with the XRD data for the parent phase BaLaInO4 [24]. The cell parameters for undoped BaLaInO4 [24] and doped Ba1.1La0.9InO3.95 [24], Ba1.1La0.9In0.5Y0.5O3.95 samples are shown in Table 2. As it was shown earlier, the acceptor doping of lanthanum sublattice Ba 2+ → La 3+ led to an increase in all unit cell parameters and the unit cell volume. The simultaneous doping Ba 2+ → La 3+ and Y 3+ → In 3+ leads to the same effect, but the increase in the unit cell volume during co-doping is bigger (~4%) compared with increase in the case of only acceptor doping (~1%). It should be noted that the compositions with a yttrium content over 50% were not singe phases (Figure 5b, line 4). After measuring the conductivity of the synthesized phase Ba1.1La0.9In0.5Y0.5O3.95 as a function of pO2 at different temperatures and high humidity, X-ray powder diffraction patterns of the pellets were obtained (Figure 5b. line 3). Decomposition, due to the highly reduced atmosphere or to the high humidity to which the materials were exposed, did not take place.  The possibility for the dissociative water incorporation from the gas phase was checked using the thermogravimetry (TG) method. The mass loss of preliminary hydrated sample Ba1.1La0.9In0.5Y0.5O4.95•nH2O was 93.5% ( Figure 6). The mass spectrometry (MS) analysis showed that all mass loss was a result of only water removal. The calculated amount of mole of water per the formula unit is presented in the Table 2. As we can see, the water uptake increases with the increasing unit cell volume. As shown earlier [31], the amount of water uptake for layered perovskites based on BaLaInO4 is determined not by the amount of oxygen vacancies but by the size of unit cell volume. The result obtained for the co-doped sample Ba1.1La0.9In0.5Y0.5O3.95 is in agreement with this statement.  The possibility for the dissociative water incorporation from the gas phase was checked using the thermogravimetry (TG) method. The mass loss of preliminary hydrated sample Ba 1.1 La 0.9 In 0.5 Y 0.5 O 4.95 ·nH 2 O was 93.5% ( Figure 6). The mass spectrometry (MS) analysis showed that all mass loss was a result of only water removal. The calculated amount of mole of water per the formula unit is presented in the Table 2. As we can see, the water uptake increases with the increasing unit cell volume. As shown earlier [31], the amount of water uptake for layered perovskites based on BaLaInO 4 is determined not by the amount of oxygen vacancies but by the size of unit cell volume. The result obtained for the co-doped sample Ba 1.

Electrical Properties
The electrical properties of the obtained sample were investigated via the impedance spectroscopy method. The comparison of Nyquist plots for undoped BaLaInO4 and doped Ba1.1La0.9In0.5Y0.5O3.95 samples is presented in Figure 7a (500 °C, dry air). As can be seen, the doping does not affect to the general view of the plots. The one semicircle starting from zero coordinates and corresponding to the bulk component (Cbulk~10 -11 F•cm -1 ) of conductivity is observed for both samples. The bulk conductivity value for the doped sample Ba1.1La0.9In0.5Y0.5O3.95 is about 4 kΩ at 500 °C in the dry air (green symbols in Figure 7a) which is higher by almost two orders of magnitude than for the undoped sample (300 kΩ, black symbols in Figure 7a). As an example of the evolution of spectra, the Nyquist plots obtained in the wet air for the composition Ba1.1La0.9In0.5Y0.5O3.95 are presented in Figure 7b. The nature of charge carriers was discovered by investigating conductivity through the variation of oxygen partial pressure. The dependencies of conductivity vs. pO2 at different temperatures for the doped sample Ba1.1La0.9In0.5Y0.5O3.95 are presented in Figure 8. The positive slope of the conductivity curves obtained in the dry oxidizing conditions (pO2 = 10 −5 − 0.21 atm) indicates the mixed ionic-electronic (hole) nature of conductivity:

Electrical Properties
The electrical properties of the obtained sample were investigated via the impedance spectroscopy method. The comparison of Nyquist plots for undoped BaLaInO 4 and doped Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 samples is presented in Figure 7a (500 • C, dry air). As can be seen, the doping does not affect to the general view of the plots. The one semicircle starting from zero coordinates and corresponding to the bulk component (C bulk~1 0 -11 F·cm -1 ) of conductivity is observed for both samples. The bulk conductivity value for the doped sample Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 is about 4 kΩ at 500 • C in the dry air (green symbols in Figure 7a) which is higher by almost two orders of magnitude than for the undoped sample (300 kΩ, black symbols in Figure 7a). As an example of the evolution of spectra, the Nyquist plots obtained in the wet air for the composition Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 are presented in Figure 7b.  The nature of charge carriers was discovered by investigating conductivity through the variation of oxygen partial pressure. The dependencies of conductivity vs. pO 2 at different temperatures for the doped sample Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 are presented in Figure 8. The The electrolytic area (pO2 = 10 −16 − 10 −5 atm) is characterized by an independence of conductivity values from oxygen partial pressure which indicates the domination of oxygen-ionic conductivity in this pO2 region. The effect of humidity in the atmosphere is shown to start below 700 °C. The conductivity values increase in the electrolytic area up to half an order of magnitude at 420 °C, which indicates the appearance of proton current carriers (Equation (3)). In the area of wet oxidizing conditions, the interaction of holes with water leads to the formation of protons: The effect of humidity of atmosphere on the transport properties was investigated at the different temperatures. The example of initial data is presented in the Figure 9a. During the measurement, the sample was held at each temperature until the resistances became constant. It can be seen that the switching from dry to wet atmosphere leads to a decrease in the resistance values, i.e., to an increase in the values of electrical conductivity. The temperature dependencies of conductivity for the doped sample Ba1.1La0.9In0.5Y0.5O3.95 obtained for the different conditions are presented in Figure 9b. The conductivity values in the dry air (filled black symbol) were higher than that in the dry Ar (filled green symbol) by about 0.3 order of magnitude. This indicates the mixed ionic-electronic nature of conductivity in the whole temperature range. An increase in the humidity of the atmosphere led to an increase in the conductivity values compared with dry conditions. The conductivity values in the wet air (open black symbol) and wet Ar (open green symbol) were the same at temperatures lower than 400 °C, indicating the domination of proton transport in this area. It should be noted that the conductivity values obtained in the Ar (pO2~10 −5 atm) were matched with the values from the electrolytic area (red symbols in Figure 8). Thus, the values obtained in the dry Ar can be considered as oxygen-ionic conductivity values. The electrolytic area (pO 2 = 10 −16 − 10 −5 atm) is characterized by an independence of conductivity values from oxygen partial pressure which indicates the domination of oxygen-ionic conductivity in this pO 2 region. The effect of humidity in the atmosphere is shown to start below 700 • C. The conductivity values increase in the electrolytic area up to half an order of magnitude at 420 • C, which indicates the appearance of proton current carriers (Equation (3)). In the area of wet oxidizing conditions, the interaction of holes with water leads to the formation of protons: The effect of humidity of atmosphere on the transport properties was investigated at the different temperatures. The example of initial data is presented in the Figure 9a. During the measurement, the sample was held at each temperature until the resistances became constant. It can be seen that the switching from dry to wet atmosphere leads to a decrease in the resistance values, i.e., to an increase in the values of electrical conductivity. The temperature dependencies of conductivity for the doped sample Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 obtained for the different conditions are presented in Figure 9b. The conductivity values in the dry air (filled black symbol) were higher than that in the dry Ar (filled green symbol) by about 0.3 order of magnitude. This indicates the mixed ionic-electronic nature of conductivity in the whole temperature range. An increase in the humidity of the atmosphere led to an increase in the conductivity values compared with dry conditions. The conductivity values in the wet air (open black symbol) and wet Ar (open green symbol) were the same at temperatures lower than 400 • C, indicating the domination of proton transport in this area. It should be noted that the conductivity values obtained in the Ar (pO 2~1 0 −5 atm) were matched with the values from the electrolytic area (red symbols in Figure 8). Thus, the values obtained in the dry Ar can be considered as oxygen-ionic conductivity values.  Figure 10 represents the comparison of temperature dependencies of conductivity obtained for the different conditions (dry/wet air and Ar). As can be seen, the conductivity increases in the row BaLaInO4-Ba1.1La0.9InO3.95-Ba1.1La0.9In0.5Y0.5O3.95 for all conditions, i.e., in the row of an increasing unit cell volume and interlayer space (space between perovskite octahedra layers). It was shown that ionic transport for layered perovskites like BaN-dInO4 [22] and BaLaScO4 [23] occurs via oxygen jumps between apical oxygens in the perovskite octahedra and oxygens in the salt layers, i.e., in the interlayer space of the layered structure. We can suggest that the same mechanism of oxygen transport is realized for the layered perovskites based on BaLaInO4.  Figure 10 represents the comparison of temperature dependencies of conductivity obtained for the different conditions (dry/wet air and Ar). As can be seen, the conductivity increases in the row BaLaInO 4 -Ba 1.1 La 0.9 InO 3.95 -Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 for all conditions, i.e., in the row of an increasing unit cell volume and interlayer space (space between perovskite octahedra layers). It was shown that ionic transport for layered perovskites like BaNdInO 4 [22] and BaLaScO 4 [23] occurs via oxygen jumps between apical oxygens in the perovskite octahedra and oxygens in the salt layers, i.e., in the interlayer space of the layered structure. We can suggest that the same mechanism of oxygen transport is realized for the layered perovskites based on BaLaInO 4 .  Figure 10 represents the comparison of temperature dependencies of conductivity obtained for the different conditions (dry/wet air and Ar). As can be seen, the conductivity increases in the row BaLaInO4-Ba1.1La0.9InO3.95-Ba1.1La0.9In0.5Y0.5O3.95 for all conditions, i.e., in the row of an increasing unit cell volume and interlayer space (space between perovskite octahedra layers). It was shown that ionic transport for layered perovskites like BaN-dInO4 [22] and BaLaScO4 [23] occurs via oxygen jumps between apical oxygens in the perovskite octahedra and oxygens in the salt layers, i.e., in the interlayer space of the layered structure. We can suggest that the same mechanism of oxygen transport is realized for the layered perovskites based on BaLaInO4. The protonic conductivity values were calculated as the difference between values obtained in the wet and dry Ar at the same temperature (Figure 11a). The tendency for conductivity to increase with the increasing unit cell volume is reproduced. However, in the row BaLaInO4-Ba1.1La0.9InO3.95-Ba1.1La0.9In0.5Y0.5O3.95 both the size of the interlayer space and the proton concentration (water uptake) increase. Accordingly, calculating the proton mobility for a correct comparison is required: where σH-proton conductivity, Ze-charge (Z = 1), cH-volume concentration of protons. As can be seen in Figure 11b, the protonic mobility increases with increasing the size of interlayer space, i.e., with increasing the space for ionic transport.  The protonic conductivity values were calculated as the difference between values obtained in the wet and dry Ar at the same temperature (Figure 11a). The tendency for conductivity to increase with the increasing unit cell volume is reproduced. However, in the row BaLaInO 4 -Ba 1.1 La 0.9 InO 3.95 -Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 both the size of the interlayer space and the proton concentration (water uptake) increase. Accordingly, calculating the proton mobility for a correct comparison is required: where σ H -proton conductivity, Ze-charge (Z = 1), c H -volume concentration of protons. As can be seen in Figure 11b, the protonic mobility increases with increasing the size of interlayer space, i.e., with increasing the space for ionic transport.  Figure 10. The temperature dependencies of conductivities for the BaLaInO4 [24] (1), Ba1.1La0.9InO3.95 [24] (2), and Ba1.1La0.9In0.5Y0.5O3.95 (3) obtained under dry air (a), dry Ar (b), wet air (c), wet Ar (d).
The protonic conductivity values were calculated as the difference between values obtained in the wet and dry Ar at the same temperature (Figure 11a). The tendency for conductivity to increase with the increasing unit cell volume is reproduced. However, in the row BaLaInO4-Ba1.1La0.9InO3.95-Ba1.1La0.9In0.5Y0.5O3.95 both the size of the interlayer space and the proton concentration (water uptake) increase. Accordingly, calculating the proton mobility for a correct comparison is required: where σH-proton conductivity, Ze-charge (Z = 1), cH-volume concentration of protons. As can be seen in Figure 11b, the protonic mobility increases with increasing the size of interlayer space, i.e., with increasing the space for ionic transport.  Therefore, the simultaneous doping of barium and indium sublattice by cations with bigger ionic radii leads to the increase of both unit cell volume and water uptake. However, the increasing the proton conductivity values occurs not only by an increase in the proton concentration but by an increase in their mobility as well. This allows us to conclude that the method of simultaneous hetero-and isovalent doping is a very prospective strategy for improving the transport properties of proton conductors with layered perovskite structures.

Conclusions
In the present work, the method of simultaneous hetero-and isovalent doping for the purpose of improving the transport properties of layered perovskites was investigated. The co-doped complex oxide Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 was prepared for the first time. It was shown that the co-doping by ions with bigger ionic radii allows for increasing the unit cell volume by up to 4% and water uptake by three times compared with an undoped BaLaInO 4 composition. The correlation of the increase in ionic conductivity with an increase in the unit cell volume and the interlayer space for layered perovskites was confirmed. The increase in the proton conductivity values obtained was both due to the increase in the proton concentration and their mobility. The sample Ba 1.1 La 0.9 In 0.5 Y 0.5 O 3.95 was nearly a pure proton conductor below 400 • C. The co-doping strategy allows for increasing the protonic conductivity values by up to two orders of magnitude and it is a successful method for the design of novel protonic conductors based on layered perovskites.