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# Microscopic ion migration in solid electrolytes revealed by terahertz time-domain spectroscopy

## Abstract

Terahertz spectroscopy is one of the most suitable methods for the analysis of electron transport in solids, and has been applied to various materials. Here, we demonstrate that terahertz spectroscopy is the technique of choice to characterize solid electrolytes. We measure the terahertz conductivity of stabilized zirconia, a widely used solid electrolyte material, by terahertz time-domain spectroscopy at high temperatures, providing a wealth of information unavailable from conventional techniques. It is found that the conductivity reflects the microscopic motion of the ion just before hopping to an unoccupied site. Our results suggest a powerful approach in probing the ionic conduction mechanism and could help us explore other solid electrolytes for fuel cells and all-solid-state batteries.

## Introduction

Terahertz (THz) conductivity measurements are one of the most powerful and popular tools in present material science to evaluate the carrier transport in solids1,2,3. At low temperatures, the electrons and holes in a doped semiconductor are trapped by the impurity atoms. Here, the resonance frequencies appear in the THz regime (typically several THz). When the carriers are thermally activated at high temperatures, the resulting free electrons and holes exhibit a large conductivity at zero frequency. Since the electronic transport in semiconductors is governed by electron–lattice scattering on the sub-picosecond timescale, the electronic conductivity has also a component in the THz frequency range4,5. The schematics of the electron transport and the corresponding conductivity spectra are shown in Fig. 1a, b, respectively. Recent advances in ultrashort laser and frequency conversion technologies have enabled coherent THz wave generation and detection2,6,7, which allows us to perform THz time-domain spectroscopy (THz-TDS) measurements with high spatio-temporal resolution without need of electrodes. THz conductivity measurements have been performed on various electronic materials including strong correlated electron systems1,4,8.

We propose THz-TDS as an advanced method for the characterization of ion transport in solid electrolytes, which is decisive for the performance of fuel cells or all-solid-state battery9,10,11. Fuel cells have been getting enormous attentions as a new energy generator, because they have various advantages such as high efficiency and cleanliness, compared to conventional power sources12,13. All-solid-state battery also has much benefits, such as higher charging speed and higher stability than the conventional batteries14. Here, we picked up the stabilized zirconia as an example of solid electrolyte. The stabilized zirconia is the one of the most popular and familiar solid electrolytes and is widely used in commercial solid oxide fuel cells (SOFCs)15,16. The ion conduction is usually interpreted in terms of hopping as shown in Fig. 1c. Acceptor dopants located at the cation sublattice in the crystal generate oxygen vacancies, and an adjacent oxygen can hop to an unoccupied site at adequately high temperatures. The energy of this potential barrier is also termed migration energy, which is one of the most important parameters for the intrinsic ion conduction17. However, even at the operating temperature of the SOFCs, some oxygen vacancies form defect clusters and stay at specific sites near the acceptor dopants18. The stability of the defect cluster is expressed with the binding energy, which strongly modulates the shape of the long-range potential of the acceptor ion. The long-range potential (also called activation energy $$E_{\mathrm{a}}^{{\mathrm{low}}}$$ indicated with the blue dashed line in Fig. 1c) is the sum of migration energy and binding energy, and can be evaluated using conventional low-frequency (<MHz) impedance measurements. The THz-TDS allows us to investigate the microscopic potential in the oxide ion conductor (that is, the potential that is involved in the hopping process indicated with the orange arrow in Fig. 1c), which is crucial for SOFC material design.

We believe the motion of the ions in the THz frequency range reflects the microscopic ion hopping. Oxygen ions near the vacancy oscillate thermally at the so-called attempt frequency (several THz) before hopping occurs. Such an ion motion can be regarded as a single vacancy mode in accordance with the picture of the hole in an electronic system. It is similar to the localized ion mode in a semiconductor19, which is different from the collective ion motion (phonon)1,20,21,22. Since the vacancy modes have strong anharmonicity23, a vacancy oscillation with a large amplitude at high temperature induces the hopping to adjacent sites. The frequency components slightly below 1 THz in the conductivity spectra become apparent at high temperatures when the amplitude of the localized vacancy mode is large24,25,26. The expected conductivity spectra at low and high temperatures are shown in Fig. 1d. Therefore, the THz conductivity in a solid electrolyte contains essential information on the individual ion hopping, which is strongly different from the information provided by the long-range low-frequency conductivity measurements.

Here, in this work, we perform THz-TDS for stabilized zirconia at high temperatures and show that the evaluated conductivity includes the information on the microscopic motion of the ion just before hopping to an unoccupied site occurs, which cannot easily be evaluated by conventional techniques.

## Results

### THz conductivity measurements

We employ THz-TDS to investigate the conductivity in yttria-stabilized zirconia Zr0.84Y0.16O2−δ (8YSZ), which is commercially used as SOFC electrolyte with the cubic fluorite structure15,27 shown in Fig. 2a. Pure ZrO2 undergoes a phase transition from the monoclinic structure to the tetragonal structure at a temperature T of about 1400 K, and transits to the cubic structure at ~2570 K27,28. The doping with 8 mol% Y2O3 enables stabilization of the zirconia’s cubic fluorite structure even at room temperature27 and simultaneously creates oxygen vacancies. Therefore, the oxygen ions can move to the vacancy site, which constitutes the ion conduction. The ion conduction in 8YSZ has been investigated by conventional impedance measurements29,30,31,32,33,34,35,36,37, and 8YSZ is actually utilized as solid electrolyte in oximeters and fuel cells15. The ion transport in 8YSZ has also been discussed theoretically17,38. Furthermore, the phonon modes have been determined by neutron scattering39,40 and Fourier infrared spectroscopy41,42.

Figure 2b shows the time profile of the reference THz pulse that is detected without the sample, and Fig. 2c shows the THz waves that are detected after the reference pulses have passed through the 370 μm-thick ceramic 8YSZ plate at different temperatures. The details of our experimental setup for the THz-TDS are described in the Methods. The amplitude of the THz pulse that is transmitted through the zirconia sample at room temperature (Fig. 2b; blue curve) is smaller than that of the incident (reference) pulse and also exhibits a retardation of 6 ps. The amplitude reduction is a result of the reflection and absorption by the sample and the time delay reflects the slow phase velocity of the THz pulse in 8YSZ22. We find that, as the sample’s temperature is increased to 1273 K the amplitude decreases further. This suggests that the absorption or conductivity in 8YSZ changes at higher temperatures.

In order to perform a quantitative analysis of the change in the conductive properties, we evaluate the THz conductivity σTHz from Fourier-transformed electric field profiles of the detected THz pulses (see Methods). Figure 3a plots the real part of the THz conductivity in 8YSZ at different temperatures under ambient atmosphere on a double-logarithmic scale. The real part of the THz conductivity and the real part of the dielectric constant are shown on a linear scale in Supplementary Fig. 1a and 1b, respectively. At room temperature, the THz conductivity increases with the frequency v. Additionally, also an increase in the temperature leads to an increase of the THz conductivity, in particular, at the lower frequency region and hence the slopes of the spectra decrease at higher temperatures. Using a single crystal, we verified that these trends hardly depend on the crystallinity (see Supplementary Fig. 2; the THz conductivity of an 8YSZ single crystal at various temperatures exhibits the same spectral shapes as that of the ceramic sample discussed here).

The origin of the THz conductivity component at high temperatures is important for the physics of the SOFC electrolyte. One may consider that this conductivity component is a result of the spectral broadening of the high-frequency phonon mode. Actually, one infrared-active transverse optical (TO) phonon mode at 7.7 THz has been theoretically predicted for the cubic zirconia crystal28. Its spectral width should be proportional to the temperature via inter-phonon scattering22,37 while maintaining $${\mathrm{\sigma }} \propto {\mathrm{\nu }}^2$$ at the frequency region below the resonance frequency. The THz conductivity spectrum at room temperature is indeed proportional to v2 (Fig. 2a). However, the slope of the spectrum decreases with temperature, and approaches $${\mathrm{\sigma }} \propto \nu$$ at high temperatures. This suggests that the spectral change is not due to the spectral broadening of the phonon.

To confirm the minor contribution of the phonon to the THz conductivity at high temperatures, we measure the THz conductivity of another zirconia sample with a Y2O3 doping concentration of 3 mol% (hereafter referred to as 3YSZ). It is known that the 3YSZ has an additional phonon resonance at 5 THz due to the tetragonal structure and exhibits a weak ion conduction compared to 8YSZ15,43. Figure 3b plots the real part of the THz conductivity in 3YSZ at various temperatures on a double-logarithmic scale. The slope of σ in the 3YSZ sample remained proportional to v2 even at T = 1273 K. This also supports that the spectral change of the THz conductivity in 8YSZ is not governed by the phonon resonance.

### Evaluation of the activation energy

Another plausible mechanism for the conductivity increase observed in Fig. 3a is the long-range ion conduction that expands toward the THz frequency region. Ion conduction in SOFC electrolytes is explained with the hopping of some oxygen ions to unoccupied sites in the lattice. Various long-range conduction models, such as the correlated barrier hopping model, have been proposed for the frequency region below GHz. These models predict a power law for the high-frequency conductivity that is similar to our results (σ = σ0 + σs)35. Similar discussions have been performed for glass systems44. The low-frequency ion conductivity σ can be analyzed with the Arrhenius model using

$$\sigma = (A/T){\mathrm{exp}}[ - E_a/k_BT]$$
(1)

where A, kB, and Ea correspond to the pre-exponential factor, the Boltzmann coefficient, and the activation energy, respectively. The red closed circles in Fig. 4a present the THz conductivity at 0.36 THz. Here, the horizontal axis expresses the inverse temperature and the vertical axis plots ln(σT). Since Eq. (1) can be rewritten as $$\ln \left( {\sigma T} \right) = - (E_a/k_B)(1/T) + {\mathrm{ln}}A$$, a straight line in this plot suggests that the conductivity obeys the Arrhenius model at high temperatures. In the low-temperature regime, the measured THz conductivity does not follow the straight line due to the phonon contribution as mentioned above. However, as elaborated in the next Section, for the present purpose it is sufficient to fit the high-temperature range. From the slope at high temperatures, we can estimate the activation energy at ν = 0.36 THz, $$E_a^{THz}$$(0.36 THz) = 0.3 eV. Furthermore, Fig. 4b evidences that the activation energy decreases as the THz frequency increases. We also show those for the 8YSZ single crystal and 3YSZ sample in Supplementary Fig. 3, and the prominent features are the same.

### Low-frequency impedance measurements

This activation energy evaluated from the THz conductivity is different from the results obtained by conventional low-frequency impedance measurements. We performed impedance measurements on an 8YSZ ceramic sample and show the Arrhenius plot of the low-frequency conductivity as the blue circles in Fig. 4a. Obviously, the slope of the low-frequency conductivity is larger than that of the THz conductivity. We evaluated an activation energy of $$E_a^{low}$$ = 1.03 eV, which is consistent with the 0.8–1.1 eV reported previously31,33,34,35. Therefore, the origin of the activation energy obtained by the THz conductivity measurement is different from that obtained by the low-frequency impedance measurements.

## Discussion

As elaborated further below, a vacancy oscillates at a specific site of the lattice until it jumps to an adjacent site. The latter process occurs at a timescale of nanoseconds or longer. This hopping mechanism suggests that the THz conductivity component is related to the large-amplitude vacancy modes, which are relevant for the vacancy hopping. These vacancies modulate phonons. While one TO phonon in cubic zirconia without dopant has been predicted at 7.7 THz28, infrared reflection spectroscopy implies a TO phonon mode at 10 to 12 THz in YSZ41,42. We also experimentally confirmed this resonance (at 11 THz, as shown in Supplementary Fig. 4). On the other hand, Shin and Ishigame et al. have revealed defect-induced modes around 9 and 21 THz by employing hyper Raman scattering spectroscopy45. These modes are infrared-active T1u modes, and have been assigned to the oxygen defect with the analysis of the O6 molecule45. Thus, we analyze the infrared-active component with the assumption of two contributions, the phonon component with low-nonlinearity and the oxygen vacancy component. Since the potentials for the vacancy modes exhibit a strong anharmonicity17,38, the vacancy jumps to the adjacent sites via large-amplitude modes after many attempts. Hence the conductivity spectrum of the vacancy mode extends to low frequencies, and the activation energy at v = 0 Hz extrapolated from the THz conductivity includes the information of the microscopic ion hopping.

Let us verify the THz conductivity originating from this vacancy motion by using the conventional analytical technique of the THz vibrational modes in an anharmonic potential25,26. While the actual shape of the potential is very complex17,38, we approximate the individual potential at each site as Morse potential, which is one of the most typical anharmonic potentials46. The energy level Ei of the i-th vibrational mode in the Morse potential can be described as $$E_i = \left( {i + 1/2} \right)h\nu _0(1 - \chi (i + 1/2))$$ in the lowest-order approximation, leading to the following transition energy between the i-th level and i+1-th level: $$E_{i,i + 1} = h\nu _{i,i + 1} = h\nu _0(1 - 2\chi (i + 1))$$. Here, v0 represents the frequency of the lowest vibrational level (i.e., the attempt frequency), and χ is the anharmonic coefficient46. In this model, the depth of the potential U is $$h\nu _0/4\chi$$, and the quantum number is limited by $$i < 1/2\chi - 1$$, which can be derived from the condition $${\mathrm{\nu }}_{{\mathrm{i}},{\mathrm{i}} + 1} > 0$$. By assuming that the population of the vibrational mode, Ni,i+1, obeys the Maxwell–Boltzmann distribution, the optical conductivity spectrum (which is directly proportional to the absorption) at the frequency v can be written as follows

$$\sigma \propto \nu \mathop {\sum }\limits_{i = 0} \left\{ {\mu _{i,i + 1}^2\left( {N_i - N_{i + 1}} \right)\gamma \left( {\nu - \nu _{i,i + 1}} \right)} \right\}$$
$$\propto \frac{{\nu \mathop {\sum }\nolimits_{i = 0} \left\{ {\left( {i + 1} \right)\left( {e^{ - \frac{{E_i}}{{k_BT}}} - e^{ - \frac{{E_{i + 1}}}{{k_BT}}}} \right)\gamma \left( {\nu - \nu _{i,i + 1}} \right)} \right\}}}{{\mathop {\sum }\nolimits_{i = 0} e^{ - \frac{{E_i}}{{k_BT}}}}},$$
(2)

where $$\mu _{i,i + 1} \propto \sqrt {i + 1}$$ represents the transition dipole moment and $${\mathrm{\gamma }}({\mathrm{\nu }} - \nu _{i,i + 1})$$ the line width of the i-th transition. If we assume that the conductivity for $${\mathrm{\nu }} < 1\,{\mathrm{THz}}$$ is mainly governed by a single transition between a certain i-th level and the i+1-th level, Eq. (2) can be simplified as

$$\sigma \propto \nu _{i + 1,i}\left( {N_{i + 1} - N_i} \right) \approx \left( {\frac{1}{{hk_BT}}} \right)e^{ - \frac{{E_i}}{{k_BT}}}$$
(3)

in the low-frequency limit of (Ei+1Ei)/kBT1. This relation is equivalent to equation (1), which was used to determine the THz activation energy from the Arrhenius plot (Fig. 4b). Therefore, the activation energy $$E_a^{THz}$$ (0.36 THz) = 0.3 eV corresponds to the energy Ei. Since the sum of zero-point vibration energy ($$h{\mathrm{\nu }}_0/2 = 0.02\,{\mathrm{eV}}$$ with the assumption of $$\nu _0 = 11\,{\mathrm{THz}}$$) and Ei in the low-frequency limit is close to the potential barrier U for ion hopping, we find U ≈ 0.32 eV.

To clarify whether the above assumptions are valid for this material or not, we simulate the spectra of the THz conductivity using the model outlined above. We set the potential depth to U = 0.32 eV, use v0 = 11 THz as experimentally estimated, and assume χ = 0.035 using the relationship $$U = h\nu _0/4\chi$$. Figure 5a shows the energy diagram of the Morse potential, and Fig. 5b shows the mode populations at 300 and 1200 K considering the Maxwell–Boltzmann distribution. We can derive the THz conductivity from the mode population using Eq. (2), and the results are shown in Fig. 5c. In the THz regime, the components of the conductivity of the localized vacancy mode increase with the temperature, and the conductivity is proportional to the frequency below 1 THz. Figure 5d is the Arrhenius plot of the calculated THz conductivity at 0.36 THz. Indeed, this figure shows a linear relation with an activation energy close to the experimental value $$E_a^{THz}$$ (0.36 THz) = 0.27 eV. We also simulated the spectra of the THz conductivity using different parameters while maintaining the potential depth. The evaluated activation energy is slightly smaller than the depth of the potential due to the temperature-dependent normalization factor $$\mathop {\sum }\limits_{i = 0} \exp \left[ { - E_i/k_BT} \right]$$ in Eq. (2). In spite of the simple potential shape, the numerical simulation reproduces the experimental results.

Next, let us specify the site whose potential barrier is reflected in the THz conductivity measurements. When the vacancy moves to a neighboring site, it passes the saddle point of the potential that lies between two cations30. An oxygen vacancy at high temperatures remains at the lowest energy site for a long time because even the thermal energy of the vacancy mode at 1000 K is significantly smaller than the energy scale of the binding energy (>0.3 eV18,47). This fact suggests that the activation energy $$E_a^{THz}$$ evaluated from the THz conductivity reflects the minimum potential barrier for the oxygen vacancy at the lowest energy site (indicated with the orange dashed line in Fig. 1c). We note that the expected potential barrier near the dopants is larger than the intrinsic migration energy due to the additional binding energy23,48. However, it has been reported that the lowest energy site of the oxygen vacancy is the second-nearest neighbor of the dopant in case of an impurity with a large ionic radius18,47. In this case, there are several equivalent sites (located like a shell around the impurity) with the same minimum energy and the vacancy can move to a neighboring site with the same energy via several paths. The potential barrier at the Zr–Zr saddle point17 is the minimum energy required for the hopping to the next equivalent site. Therefore, we consider that activation energy determined by the THz conductivity measurements reflects the intrinsic migration energy of the oxygen vacancy.

The abovementioned migration and binding energies, which are relevant for microscopic ion conduction, have been investigated extensively, but the exact values are still a matter of debate in theoretical studies30,48. Both parameters have been characterized experimentally using the temperature-dependent slopes of the Arrhenius plots for the low-frequency conductivity49,50. However, the evaluated values are likely to exhibit a large uncertainty due to a simplified analysis, leading to unresolved issues even in zirconia16. The mechanisms of oxide ion migration (e.g. the formation of oxygen vacancies and their preferential locations) have also been investigated by nuclear magnetic resonance51, and muon measurements52. However, these are not standard techniques that are easily accessible for a wide range of researchers. Here, we applied a standard technique based on ultrashort optical pulse technology and directly evaluated the oxide ion dynamics in the solid electrolyte of SOFC. This method enables the direct evaluation of the charge fluctuation owning to its high temporal resolution. Our proposed method is very attractive for the field of ionics, because the intrinsic migration energy of the oxygen vacancy can be accurately measured. We measured the THz conductivity for different stabilized zirconia samples to investigate the dependence of the activation energy on the impurity atom type (M2O3 with M = Y, Yb, Gd, Sc, and MO2 with M = Ca, Mg). Figure 6a shows the activation energies evaluated by the low-frequency impedance method, $$E_a^{low}$$. The temperature dependence of the low-frequency impedance is shown in Supplementary Fig. 5. Figure 6b shows the activation energies evaluated by the THz conductivity measurements at $${\mathrm{\nu }} = 0.36\,{\mathrm{THz}}$$, $$E_a^{THz}$$. The graph clearly shows that the THz activation energy decreases with the ionic radius of the dopant, which is different from the result obtained in the impedance measurements. This is because the activation energy obtained in the impedance measurement reflects the long-range potential while the THz activation energy reflects the short-range potential. The trend of the THz activation energy is a result of the increase in the effective lattice constant due to the larger ionic radius of the dopant. Therefore, the migration energy along the Zr–Zr path decreases17,48. This tendency is in good agreement with the calculation result17.

In conclusion, we measured the THz conductivity of various stabilized zirconia samples by THz-TDS. We observed the THz responses originating from the large-amplitude oxygen-vacancy motion, which is related to the vacancy hopping to adjacent sites. The temperature dependence of the THz conductivity revealed the intrinsic migration energy of the vacancy. This method is applicable to various solid electrolytes in protonic ceramic fuel cells (PCFC)53,54,55,56,57 and all-solid-state lithium ion batteries10,58, because the attempt frequencies of the ion transport in these materials are also expected to lie around several THz59. Since THz-TDS should reveal the hidden mechanism of ionic conduction, our proposed method is useful for development of novel solid electrolytes for fuel cells or all-solid-state batteries.

## Methods

### Sample preparation

The Zr0.84Y0.16O2-δ and Zr0.88Sc0.12O2-δ pellets were prepared using commercial powder. The Zr0.84Y0.16O2-δ powder (TOSOH) and the Zr0.88Sc0.12O2-δ powder (DAIICHI KIGENSO KAGAKU KOGYO) were first pressed into pellets at 250 MPa and then sintered at 1673 K for 5 and 2 h in air, respectively. The Zr0.84M0.16O2-δ (M=Mg, Yb, Ca) samples were prepared by a solid-state reaction method (SSR). The reagent-grade ZrO2 (99.9 %), MgO(99.9%), Yb2O3 (99.9 %), and CaCO3 (99.9 %) powders were weighed and mixed in ethanol using a mortar and a pestle. The powder mixtures were calcined in air for 5 h at 1273 K. The calcined Zr0.84M0.16O2-δ (M = Mg, Yb, Ca) powders were ball-milled and pressed into pellets at 250 MPa and then sintered at 1873 K for 5 h in air. The Zr0.84Gd0.16O2-δ pellets with single phase were prepared by a combustion synthesis method. ZrO(NO3)3 2.1H2O(99.9 %), Gd(NO3)3 6.1H2O (99.9 %), water, citric acid, and ethylenediamine tetraacetice acid were mixed while maintaining a pH of 10 by adding aqueous ammonia. After ammonium nitrate was added, the solution was heated at 623 K. The obtained powders were calcined in air for 10 h at 1173 K. The powder was further ball-milled and pressed into CIP pellets at 250 MPa, which was followed by sintering at 1873 K for 10 h in air. The obtained samples were used for both the THz conductivity measurements and the impedance measurements. For characterization, we measured the X-ray diffraction (XRD) of the powder samples using MinFlex600 (Rigaku) with CuKα radiation. All XRD patterns shown in Supplementary Fig. 6 were analyzed by employing the Rietveld refinement technique. The X-ray powder diffraction analysis confirmed a well-defined fluorite pattern for all samples prepared in this study.

### Experimental setup for the THz time-domain spectroscopy

We performed the THz-TDS measurements by using the output from an Er-doped fiber laser (TOPTICA Photonics, FemtoFiber pro NIR) with a center wavelength of 780 nm (second harmonic of 1560 nm), a repetition rate of 80 MHz, an average power of 130 mW, and a pulse duration of 90 fs. A beam splitter was used to divide the output beam into the excitation beam for THz pulse generation and the sampling beam for detection, respectively. The excitation pulse was focused on an InAs plate exposed to a magnetic field of 0.5 T. The THz pulses emitted from InAs were guided by four parabolic mirrors to the sample and transmitted to an electro-optic (EO) detector, which was a 1-mm-thick (110)-oriented ZnTe crystal. The instantaneous THz electric field amplitude alters the birefringence of the ZnTe crystal. The sampling pulses were focused on the same crystal, and the polarization state of the sampling pulse modulated by the THz wave was measured using a quarter wave plate, a Wolston prism, and balanced Si detectors. To achieve a high signal-to-noise ratio in the measurements, the excitation pulses were chopped at 6 kHz and the modulated signal was analyzed with a lock-in amplifier. The sample was placed in an electric furnace with temperatures up to 1300 K under atmosphere without dry-gas replacement, and the THz pulse entered the furnace through an aperture with 7 mm diameter (no window) using an off-axis parabolic mirror. This setup has a low-frequency detection limit of 0.35 THz. The black-body radiation from the sample can hardly influence our measurements because its field amplitude is much lower than that of the coherent THz pulse. Nevertheless, we carefully blocked the black-body radiation from the electric furnace with thin black polypropylene films.

### Evaluation of complex optical conductivity

Using THz-TDS, we determined the electric field waveform of the THz pulse transmitted through the sample, $$E_s(t)$$, and that of the reference pulse without sample, $$E_r\left( t \right)$$. The complex optical conductivity $$\tilde \sigma (\omega )$$ can directly be evaluated with these time profiles as explained in the following. First, we only employ the measured electric field waveforms in the time region from 2 to 16 ps, because the signal at 18 ps caused by multiple reflections in the sample complicates the analysis. Second, the complex transmittance $$\tilde t\left( \omega \right)$$, which is a ratio between the Fourier-transformed electric fields $$\tilde E_s\left( \omega \right)$$ and $$\tilde E_r\left( \omega \right)$$, can simply be expressed in terms of the complex permittivity $$\tilde \varepsilon (\omega )$$,

$$\tilde t\left( \omega \right) = \frac{{\tilde E_s\left( \omega \right)}}{{\tilde E_r\left( \omega \right)}} = \frac{{4\sqrt {\tilde \varepsilon (\omega )} }}{{\left( {\sqrt {\tilde \varepsilon (\omega )} + 1} \right)^2}}\exp \left[ {\frac{{i\left( {\sqrt {\tilde \varepsilon (\omega )} - 1} \right)d\omega }}{c}} \right]$$
(4)

Here, c is the speed of light (in vacuum) and d is the sample thickness. Thus, we can obtain $$\tilde \varepsilon (\omega )$$ from $$\tilde t\left( \omega \right)$$ and then evaluate the complex conductivity $$\tilde \sigma (\omega )$$ using the following relation,

$$\tilde \varepsilon \left( {\mathrm{\omega }} \right) = \varepsilon _\infty + \frac{{\tilde \sigma \left( \omega \right)}}{{i\omega }}$$
(5)

### Impedance analysis

The electrical conductivities of the samples were measured by a two-probe alternating-current technique. The samples prepared for this measurement had the shape of a pellet (length: 0.5–1.0 mm). The Pt electrodes were prepared by applying a Pt paste on both surfaces of the pellet and subsequent baking at 1173 K in air. The samples were equilibrated with 1.9% H2O–21% O2–Ar in the temperature range of 573–1073 K. The complex impedance was measured in the frequency range of 4–8 MHz using an inductance–capacitance–resistance meter (HIOKI corporation: IM3536).

## Data availability

All data needed to evaluate the conclusions in the paper are present in the paper and/or its Supplementary Information. All other data are available from the corresponding author upon reasonable request.

## References

1. Ferguson, B. & Zhang, X. C. Materials for terahertz science and technology. Nat. Mater. 1, 26–33 (2002).

2. Tonouchi, M. Cutting-edge terahertz technology. Nat. Photonics 1, 97–105 (2007).

3. Dhillon, S. S. et al. The2017 terahertz science and technology roadmap. J. Phys. D. Appl. Phys. 50, 043001 (2017).

4. Grischkowsky, D., Keiding, S., van Exter, M. & Fattinger, C. Far-infrared time-domain spectroscopy with terahertz beams of dielectrics and semiconductors. J. Opt. Soc. Am. B 7, 2006–2015 (1990).

5. Lloyd-Hughes, J. & Jeon, T. I. A review of the terahertz conductivity of bulk and nano-materials. J. Infrared, Millim., Terahertz Waves 33, 871–925 (2012).

6. Sakai, K. Terahertz Optoelectronics. (Springer, Berlin, 2005).

7. Mittleman, D. M. Frontiers in terahertz sources and plasmonics. Nat. Photonics 7, 666–669 (2013).

8. Huber, R. et al. How many-particle interactions develop after ultrafast excitation of an electron-hole plasma. Nature 414, 286–289 (2001).

9. Steele, B. C. H. & Heinzel, A. Materials for fuel-cell technologies. Nature 414, 345–352 (2001).

10. Kamaya, N. et al. A lithium superionic conductor. Nat. Mater. 10, 682–686 (2011).

11. Knauth, P. Inorganic solid Li ion conductors: an overview. Solid State Ion. 180, 911–916 (2009).

12. Mahato, N., Banerjee, A., Gupta, A., Omar, S. & Balani, K. Progress in material selection for solid oxide fuel cell technology: a review. Prog. Mater. Sci. 72, 141–337 (2015).

13. Minh, N. Q. Ceramic fuel cells. J. Am. Ceram. Soc. 76, 563–588 (1993).

14. Sun, C., Liu, J., Gong, Y., Wilkinson, D. P. & Zhang, J. Recent advances in all-solid-state rechargeable lithium batteries. Nano Energy 33, 363–386 (2017).

15. Weber, A. & Ivers-Tiffée, E. Materials and concepts for solid oxide fuel cells (SOFCs) in stationary and mobile applications. J. Power Sources 127, 273–283 (2004).

16. Kharton, V. V., Marques, F. M. B. & Atkinson, A. Transport properties of solid oxide electrolyte ceramics: a brief review. Solid State Ion. 174, 135–149 (2004).

17. Pornprasertsuk, R., Ramanarayanan, P., Musgrave, C. B. & Prinz, F. B. Predicting ionic conductivity of solid oxide fuel cell electrolyte from first principles. J. Appl. Phys. 98, 103513 (2005).

18. Zacate, M. O., Minervini, L., Bradfield, D. J., Grimes, R. W. & Sickafus, K. E. Defect cluster formation in M2O3-doped cubic ZrO2. Solid State Ion. 128, 243–254 (2000).

19. Klingshirn, C. Semiconductor Optics. (Springer, Berlin, 2005).

20. Stoyanov, N. S., Ward, D. W., Feurer, T. & Nelson, K. A. Terahertz polariton propagation in patterned materials. Nat. Mater. 1, 95–98 (2002).

21. Feurer, T., Vaughan, J. C. & Nelson, K. A. Spatiotemporal coherent control of lattice vibrational waves. Science 299, 374–377 (2003).

22. Ichikawa, Y., Nagai, M. & Tanaka, K. Direct observation of the soft-mode dispersion in the incipient ferroelectric KTaO3. Phys. Rev. B—Condens. Matter Mater. Phys. 71, 092106 (2005).

23. Eichler, A. Tetragonal Y-doped zirconia: structure and ion conductivity. Phys. Rev. B—Condens. Matter Mater. Phys. 64, 174103 (2001).

24. Walther, M., Fischer, B. M. & Jepsen, P. U. Noncovalent intermolecular forces in polycrystalline and amorphous saccharides in the far infrared. Chem. Phys. 288, 261–268 (2003).

25. Korter, T. M. & Plusquellic, D. F. Continuous-wave terahertz spectroscopy of biotin: vibrational anharmonicity in the far-infrared. Chem. Phys. Lett. 385, 45–51 (2004).

26. Jewariya, M., Nagai, M. & Tanaka, K. Ladder climbing on the anharmonic intermolecular potential in an amino acid microcrystal via an intense monocycle terahertz pulse. Phys. Rev. Lett. 105, 203003 (2010).

27. Liu, T., Zhang, X., Wang, X., Yu, J. & Li, L. A review of zirconia-based solid electrolytes. Ionics 22, 2249–2262 (2016).

28. Zhao, X. & Vanderbilt, D. Phonons and lattice dielectric properties of zirconia. Phys. Rev. B—Condens. Matter Mater. Phys. 65, 075105 (2002).

29. Abelard, P. & Baumard, J. F. Study of the dc and ac electrical properties of an yttria-stabilized zirconia single crystal [(ZrO2)0.88-(Y2O3)0.12]. Phys. Rev. B 26, 1005–1017 (1982).

30. Kilner, J. A. & Brook, R. J. A study of oxygen ion conductivity in doped non-stoichiometric oxides. Solid State Ion. 6, 237–252 (1982).

31. Badwal, S. P. S. Electrical conductivity of single crystal and polycrystalline yttria-stabilized zirconia. J. Mater. Sci. 19, 1767–1776 (1984).

32. Stafford, R. J., Rothman, S. J. & Routbort, J. L. Effect of dopant size on the ionic conductivity of cubic stabilised ZrO2. Solid State Ion. 37, 67–72 (1989).

33. Ciacchi, F. T., Crane, K. M. & Badwal, S. P. S. Evaluation of commercial zirconia powders for solid oxide fuel cells. Solid State Ion. 73, 49–61 (1994).

34. Filal, M., Petot, C., Mokchah, M., Chateau, C. & Carpentier, J. L. Ionic conductivity of yttrium-doped zirconia and the ‘composite effect’. Solid State Ion. 80, 27–35 (1995).

35. Pimenov, A., Ullrich, J., Lunkenheimer, P., Loidl, A. & Ruscher, C. H. Ionic conductivity and relaxations in ZrO2–Y2O3 solid solutions. Solid State Ion. 109, 111–118 (1998).

36. Yamamoto, O. et al. Zirconia based oxide ion conductors for solid oxide fuel cells. Ionics 4, 403–408 (1998).

37. Teranishi, T. et al. Complex conductivity using wideband spectroscopy for yttria/ytterbia- stabilized zirconia ceramics. Jpn. J. Appl. Phys. 51, 011102 (2012).

38. Shimojo, F., Okabe, T., Tachibana, F., Kobayashi, M. & Okazaki, H. Molecular dynamics studies of yttria stabilized zirconia: I. Structure and oxygen diffusion. J. Phys. Soc. Jpn. 61, 2848–2857 (1992).

39. Elcombet, M. A neutron scattering investigation of Cubic Stabilised Zirconia (CSZ)—II. Lattice dynamics of Y- and Ca-CSZ. J. Phys. Chem. Solids 57, 343–351 (1996).

40. Cousland, G. P. et al. Investigation of the vibrational properties of cubic yttria-stabilized zirconia: a combined experimental and theoretical study. J. Phys. Chem. Solids 75, 351–357 (2014).

41. Liu, D. W., Perry, C. H. & Ingel, R. P. Infrared spectra in nonstoichiometric yttria-stabilized zirconia mixed crystals at elevated temperatures. J. Appl. Phys. 64, 1413–1417 (1988).

42. Artemov, V. G. et al. Analysis of electric properties of ZrO2-Y2O3 single crystals using teraherz IR and impedance spectroscopy techniques. Russ. J. Electrochem. 50, 690–693 (2014).

43. Feinberg, A. & Perry, C. H. Structural disorder and phase transitions in ZrO2-Y2O3 system. J. Phys. Chem. Solids 42, 513–518 (1981).

44. Krishnaswami, S., Jain, H., Kamitsos, E. I. & Kapoutsis, J. A. Connection between the microwave and far infrared conductivity of oxide glasses. J. Non Cryst. Solids 274, 307–312 (2000).

45. Shin, S. & Ishigame, M. Defect-induced hyper-Raman spectra in cubic zirconia. Phys. Rev. B 34, 8875–8882 (1986).

46. Haken, H. & Wolf, H. C. Molecular Physics and Elements of Quantum Chemistry. (Springer, Berlin, 1995).

47. Khan, M. S., Islam, M. S. & Bates, D. R. Cation doping and oxygen diffusion in zirconia: a combined atomistic simulation and molecular dynamics study. J. Mater. Chem. 8, 2299–2307 (1998).

48. Nakayama, Masanobu & Martion., Manfred First-principles study on defect chemistry and migration of oxide ions in ceria doped with rare-earth cations. Phys. Chem. Chem. Phys. 11, 3241 (2009).

49. Bauerle, J. E. & Hrizo, J. Interpretation of the resistivity temperature dependence of high purity (ZrO2)0.90(Y2O3)0.10. J. Phys. Chem. Solids 30, 565–570 (1969).

50. Omar, S., Wachsman, E. D., Jones, J. L. & Nino, J. C. Crystal structure-ionic conductivity relationships in doped ceria systems. J. Am. Ceram. Soc. 92, 2674–2681 (2009).

51. Kawata, K., Maekawa, H., Nemoto, T. & Yamamura, T. Local structure analysis of YSZ by Y-89 MAS-NMR. Solid State Ion. 177, 1687–1690 (2006).

52. Vieira, R. B. L. et al. Muon-Spin-rotation study of yttria-stabilized zirconia (ZrO2:Y): evidence for muon and electron separate traps. J. Phys. Conf. Ser. 551, 012050 (2014).

53. Duan, C. et al. Readily processed protonic ceramic fuel cells with high performance at low temperatures. Science 349, 1321–1326 (2015).

54. Kreuer, K. D. Proton-conducting oxides. Annu. Rev. Mater. Res. 33, 333–359 (2003).

55. Bae, K. et al. Demonstrating the potential of yttrium-doped barium zirconate electrolyte for high-performance fuel cells. Nat. Commun. 8, 14553 (2017).

56. An, H. et al. A 5 × 5 cm2 protonic ceramic fuel cell with a power density of 1.3 W cm−2 at 600 °C. Nat. Energy 3, 870–875 (2018).

57. Choi, S. et al. Exceptional power density and stability at intermediate temperatures in protonic ceramic fuel cells. Nat. Energy 3, 202–210 (2018).

58. Kawasoko, H., Shiraki, S., Suzuki, T., Shimizu, R. & Hitosugi, T. Extremely low resistance of Li3 PO4 electrolyte/Li(Ni0.5 Mn1.5)O4 electrode interfaces. ACS Appl. Mater. Interfaces 10, 27498–27502 (2018).

59. Bachman, J. C. et al. Inorganic solid-state electrolytes for lithium batteries: mechanisms and properties governing ion conduction. Chem. Rev. 116, 140–162 (2016).

## Acknowledgements

This work was partially supported by JSPS KAKENHI (Grant Numbers JP17J04949, JP15H03579, JP18H05212) and the Ministry of Education, Culture, Sports, Science and Technology under Program for Leading Graduate Schools “Interactive Materials Science Cadet Program”.

## Author information

Authors

### Contributions

T.M. performed the experiments, data analysis, and wrote the initial draft. M.N. co-directed the scientific research, provided advice for the THz spectroscopy and data analysis, and wrote the manuscript. T.M. and M.N. developed the theoretical model with assistance from Y.M. M.A provided advice for the THz spectroscopy and the project direction. Y.Y. developed the electric furnace for the THz spectroscopy. Y.O. prepared some oxide ion conductors and performed X-ray diffraction and impedance measurements. Y.K. conceived the idea of utilizing THz spectroscopy for characterization of solid electrolytes, co-directed the scientific research, organized the joint research project, and prepared some oxide ion conductors. All authors contributed to the discussions for this manuscript and wrote parts of the manuscript.

### Corresponding authors

Correspondence to Masaya Nagai or Masaaki Ashida.

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### Competing interests

The authors declare no competing interests.

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Morimoto, T., Nagai, M., Minowa, Y. et al. Microscopic ion migration in solid electrolytes revealed by terahertz time-domain spectroscopy. Nat Commun 10, 2662 (2019). https://doi.org/10.1038/s41467-019-10501-9

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• DOI: https://doi.org/10.1038/s41467-019-10501-9

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