The Effect of Ferroelectric BaTiO3 Particles on Interfacial Resistance Between the Li-Ni-Mn-(Cr) Oxide (LNM) Spinel Cathode and Lipon
Authors: Kaneko Masakazu , Ishii Yosuke , West William Clark , Motoyama Munekazu , Iriyama Yasutoshi 
Published: February 2020

Introduction

The specific energy (Wh/kg) of a battery can be increased by increasing cell voltage. The 5V-class cathode including the Li-Ni-Mn-(Cr) oxide (LNM) spinel offers higher voltage operation relative to other widely-used Li-ion cathodes. Some inorganic solid electrolytes are known to have a wide potential window and are able to suppress electrolyte decomposition at severe anodic oxidation voltages. Thus, this 5V-class all-solid-state rechargeable lithium batteries is anticipated to be high-energy storage devices with sufficient safety.
However, large interfacial resistance at the electrode/solid electrolyte decreases the power density of the battery. It has been suggested that the large charge transfer resistance is due to the formation of space charge layer at the electrolyte side of the interface in which lithium ion is depleted and ionic conductivity is low[1][2]. To overcome this problem, we examined the interface modification by adding single crystalline nano-sized ferroelectric material, BaTiO3, between the LNM cathode and the solid electrolyte. We found that the charge transfer resistance is effectively reduced by this modification and highly-conductive regions where lithium ions easily migrate might be formed around the BaTiO3particles.

Experimental

Thin films of LiNi0.45Mn1.485Cr0.05O4 (LNM) were deposited on Ti/Pt coated silica substrates using pulsed laser deposition to a nominal cathode thickness of 30 nm. Single crystalline BaTiO3 nanoparticles (BTNs) with approximately 100 nm in diameter were deposited on LNM cathodes by means of electrospray deposition from a suspension of BTNs in 2-methoxyethanol solvent. The amount of BTNs deposited on LNM was controlled by regulating the volumes of dispersed precursor liquids. The resultant BTNs-dispersed LNM films were observed by FE-SEM. The lithium phosphorous oxynitride (LiPON) electrolyte thin films were deposited by RF magnetron sputtering and Li anode films were thermally evaporated from Li foil. Typical electrolyte and anode film thickness were 2.5 μm and 1 μm, respectively. Electrochemical properties of the resultant thin film batteries were investigated by cyclic voltammetry at a sweep rate of 1 mV/s and impedance spectroscopy over the frequency range of 200 kHz to 10 mHz. Impedance spectroscopy studies were also conducted from 283 - 416 K to measure the activation energy of the charge transfer reaction and investigate the effect of Curie temperature of BaTiO3(ca. 393 K).

Results and Discussion

FE-SEM images of LNM surfaces with the deposited BTNs were analyzed using image processing program ImageJ to measure BTNs coverage (Cov). Figure 1 (Left) shows the potential sweep curves of the batteries. The battery without BTNs modification did not show any distinct redox peak at 4.7 V, while the partially BTNs modified batteries showed oxidation peaks at 4.7 V and reduction peaks shifted depending on the amount of BTNs. Impedance analysis confirmed that the charge transfer resistances at the LiPON/LNM were effectively reduced by the partial BTNs modification, which improves the redox reactions of the batteries.
We also investigated the temperature dependency of charge transfer resistance at the LNM/LiPON interface at 4.7 V for batteries with and without BTNs modification to measure the activation energies of charge transfer. Below the Curie temperature of BaTiO3, the activation energy without BTNs modification was 60 kJ/mol, while the activation energy with BTNs modification decreased to 48 kJ/mol. Taking into account these results, it would appear that the regions where lithium ions could easily migrate might be formed around modified BTNs at the LiPON/LNM interface. Furthermore, the effects of Curie temperature were examined. When the temperature was increased above the Curie temperature of ca. 387 K, the data showed a different trend than what was observed from 298 to 377 K as shown in Figure 1 (Right), in that the interfacial resistance did not decrease above the Curie temperature as it was observed below the Curie temperature.
There are two possible mechanisms which could explain these different trends. One is the effect of Curie temperature. As a result of increasing the temperature above the Curie temperature, the ferroelectric properties of BTNs should vanish and dielectric properties of BTNs should appear. The other possible mechanism is dielectric breakdown. Because it is known that dielectric breakdown voltage of BaTiO3 decreases as temperature rises[3], dielectric breakdown is much easier for BTNs to take place. The different trends below and above Curie temperature would be due to the effect of ferroelectricity or dielectric breakdown of BTNs. The details will be presented in subsequent publications.

References

[1] N. Ohta et al., Adv. Mater., 18, 2226 (2006).
[2] C. Yada et al., Adv. Energy Mater., 4, 1301416 (2014).
[3] A. Branwood et al., J. Appl. Phys., 13, 528 (1962).

Figure 1