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. 2022 Sep 7;22(18):7477–7483. doi: 10.1021/acs.nanolett.2c02426

LiNi0.5Mn1.5O4 Cathode Microstructure for All-Solid-State Batteries

Hyeon Jeong Lee ‡,¶,§, Xiaoxiao Liu ‡,∥, Yvonne Chart ‡,, Peng Tang ‡, Jin-Gyu Bae ⊥, Sudarshan Narayanan ‡,, Ji Hoon Lee ⊥, Richard J Potter #, Yongming Sun ∥, Mauro Pasta ‡,¶,*
PMCID: PMC9523706  PMID: 36069205

Abstract

graphic file with name nl2c02426_0005.jpg

Solid-state batteries (SSBs) have received attention as a next-generation energy storage technology due to their potential to superior deliver energy density and safety compared to commercial Li-ion batteries. One of the main challenges limiting their practical implementation is the rapid capacity decay caused by the loss of contact between the cathode active material and the solid electrolyte upon cycling. Here, we use the promising high-voltage, low-cost LiNi0.5Mn1.5O4 (LNMO) as a model system to demonstrate the importance of the cathode microstructure in SSBs. We design Al2O3-coated LNMO particles with a hollow microstructure aimed at suppressing electrolyte decomposition, minimizing volume change during cycling, and shortening the Li diffusion pathway to achieve maximum cathode utilization. When cycled with a Li6PS5Cl solid electrolyte, we demonstrate a capacity retention above 70% after 100 cycles, with an active material loading of 27 mg cm–2 (2.2 mAh cm–2) at a current density of 0.8 mA cm–2.

Keywords: cathode microstructure, solid-state batteries, areal capacities, high-voltage cathodes, interfaces

Solid-state batteries (SSBs) are one of the most promising “beyond Li-ion” battery chemistries as they promise to fulfill the energy density, fast charging, and safety requirements of the future of electric transportation.1,2 The discovery of solid sulfide inorganic ceramic electrolytes in the early 2010s, with conductivities comparable to that of their liquid counterpart and mechanical properties amenable to scalable manufacturing, has further boosted the commercial interest in SSBs.3−5

Unfortunately, there are still several issues preventing SSBs from realizing their full potential.6,7 One of the most problematic challenges is the rapid capacity fade caused by the loss of contact between the Li-ion conductive solid electrolyte matrix and the active material in the composite cathode, which is triggered by volume changes that occur upon lithiation and delithiation.8−10 In addition, hoop stresses generated in the delithiated polycrystalline cathode as a result of the volume change of misoriented primary particles cause the formation of internal cracks.11 While these newly formed interfaces can be accessed by a liquid electrolyte, the limited plasticity of solid electrolytes prevents them from doing so, leading to continuous capacity decay.12,13 Low-strain cathodes have been reported to mitigate this problem by minimizing volume changes during cycling.14−17 Unfortunately, the existing low-strain cathode chemistries are incompatible with the energy density and cost requirements of commercial batteries. An alternative solution is represented by the microstructural design of high-energy cathode chemistries to mitigate the detrimental effects of volume expansion and achieve stable cycling.18

LiNi0.5Mn1.5O4 (LNMO) is one of the most promising cathode materials for next-generation lithium batteries due to its low cost (i.e., Co-free and Mn-rich) and high energy density (146 mAh g–1 theoretical capacity delivered at 4.7 V vs Li+/Li).19,20 The high operating potential of LNMO inevitably induces undesirable side reactions with a typical solid sulfide electrolyte, leading to the formation of highly resistive interphases.21−23 In addition, the volume change of LNMO during cycling is approximately 6.2%, which is higher than those of Ni-rich LiNixMnyCozO2 (NMC) cathodes (5.1% for NMC811), thus making it an attractive model system for investigating the importance of microstructure design for SSBs.24−27

In this study, we introduce Al2O3-coated LNMO secondary particles designed to have a hollow microstructure and evaluate their electrochemical performance in an all-solid-state configuration (Figure 1a). Argyrodite Li6PS5Cl (LPSCl) was selected as the solid electrolyte because of its high ionic conductivity, inherent softness, and ability to form stable electrode–electrolyte interphases.28−30 A Li0.25-In0.75 (Li–In) alloy anode was used to mitigate interfacial issues commonly reported for metallic lithium and isolate the degradation mechanisms occurring at the cathode.22,31 The shortened Li-ion diffusion length of the hollow structure facilitates uniform Li-ion extraction and prevents internal stress from accumulating in the particle.11,18,32 The Al2O3 layer deposited by atomic layer deposition (ALD) effectively attenuates the interfacial side reaction with the solid LPSCl electrolyte, thus enabling stable cycling even at high operating potentials. The combination of the Al2O3 capping layer and the hollow microstructure alleviates the volume change of the LNMO particles, thus improving the long-term cyclability of the SSB. Cathode composites prepared by a scalable dry-milling process demonstrate capacity retention above 70% after 100 cycles, with an active material loading of 27 mg cm–2 (2.2 mAh cm–2) at a current density of 0.8 mA cm–2. To the best of our knowledge, this is the top-performing LNMO cathode in a SSB configuration.

Figure 1.

Figure 1

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(a) Schematic illustration of the Al2O3-coated H-LNMO in the composite cathode of SSBs. (b) XRD pattern of H-LNMO. (c) SEM image of the synthesized H-LNMO particles and cross-section SEM image of the H-LNMO particles after FIB sectioning.

Hollow LNMO (H-LNMO) particles were synthesized via a two-step method previously reported by our group and described in detail in the Methods section of the Supporting Information.18 X-ray powder diffraction (XRD) of the as-synthesized H-LNMO particles confirms the synthesis of phase-pure LNMO with its characteristic cubic crystal structure (Figure 1b).18,33,34 Scanning electron microscopy (SEM) images show spherical secondary particles of H-LNMO that are a few micrometers in diameter and composed of plate-shaped primary particles with a size of about 500 nm (Figure 1c). SEM images of H-LNMO particles cross-sectioned by a focused ion beam (FIB) confirmed their hollow morphology and a shell thickness of approximately 400 nm (Figure 1c). Dynamic light scattering (DLS) analysis of the as-synthesized powder (Figure S1) showed D50 and D90 values of 3.62 and 5.29 μm, respectively, which are consistent with SEM observations.

Composite cathodes were prepared by mixing H-LNMO, LPSCl, and vapor-grown carbon fiber (VCF) in a weight ratio of 40:55:5, followed by a densification step at a uniaxial pressure of 500 MPa (see Methods section of the Supporting Information). Cross-section SEM images of the composite cathode show the intimate interfacial contact between H-LNMO and LPSCl and confirm that the hollow microstructure of LNMO was maintained after the densification step (Figure 2a). Energy dispersive X-ray spectroscopy (EDS) elemental mapping corroborates the homogeneous mixing of each component, which induces the formation of sufficient conduction pathways for both electrons and Li-ions (Figure 2b).

Figure 2.

Figure 2

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(a) Cross-section SEM image and (b) EDS elemental mappings of the H-LNMO/LPSCl/VCF (40:55:5) cathode composite. (c) GCD curves of SSBs with a H-LNMO composite (40:55:5) cycled at a rate of 0.1 C. (d) Comparative GCD curves of SSBs with H-LNMO and PC-LNMO composites at a rate of 0.1 C. Ex-situ XANES spectra measured at the Ni K edge of (e) PC-LNMO and (f) H-LNMO in pristine, 3.4, 4.0, 4.4 (fully charged), and 2.75 V (fully discharged) states.

The electrochemical performance of the H-LNMO composite cathode was tested in a two-electrode setup, where a Li–In alloy acted as both the reference and counter electrodes and a LPSCl pellet acted as the solid electrolyte separator (see the Methods section of the Supporting Information). Galvanostatic charge–discharge (GCD) curves of the H-LNMO composite cathode exhibit a first discharge capacity of 83.4 mAh g–1 with an initial Coulombic efficiency of 60.3%, as shown in Figure 2c. The two plateaus at 4.0 and 3.4 V (vs Li+/Li–In) correspond to the reduction of Ni4+ to Ni2+ and that of Mn4+ to Mn3+, respectively.35,36 The excess capacity on charge in the first cycle was attributed to LPSCl and VCF reacting at about 3.5 V to form a cathode–electrolyte interphase (CEI) composed of LiCl, S, and P2Sx, which can act as a passivation layer in subsequent cycles.37,38 The GCD profile of the composite cathode without VCF confirms the absence of VCF-LPSCl side reactions (Figure S2).

In order to evaluate the effect of the hollow microstructure, the electrochemical properties of H-LNMO were compared to commercial polycrystalline LNMO (PC-LNMO). PC-LNMO secondary particles have a median particle size of 11 μm and are composed of primary particles with a size of 700 nm (Figure S3). They exhibited a discharge capacity of 10.1 mAh g–1 at a rate of 0.1 C and high voltage hysteresis (Figure 2d). We believe this behavior can be attributed to the longer diffusion length in PC-LNMO compared to that in the H-LNMO. This results in the faster formation of the Li-ion concentration gradient and consequently sets up an early trigger of the cutoff voltage. In addition, the larger particle size of PC-LNMO provides less contact area between the electrode particles and the solid electrolyte particles, which results in limited reaction kinetics and thus leads to a high overpotential and a reduced discharge capacity12,39 (Figure S4). Ex situ X-ray absorption near edge structure (XANES) analysis conducted on the pristine, charged, and discharged states of PC-LNMO and H-LNMO confirm the reversible redox activity of Ni (Figures 2e and f). However, the Ni redox swing in PC-LNMO is narrower than that in H-LNMO, thus confirming its partial (de)lithiation. To further clarify the effect of a shortened diffusion path in H-LNMO, single-crystalline LNMO (SC-LNMO, MTI) with a particle size of 3.8 μm was also electrochemically evaluated. SC-LNMO showed a discharge capacity of 21.1 mAh g–1 at a rate of 0.1 C, which was still far below the the discharge capacity of H-LNMO, again highlighting the effect of the hollow microstructure of H-LNMO (Figure S5).

To mitigate the side reaction with LPSCl and increase the Coulombic efficiency, H-LNMO particles were coated with nanometer-thick layers of Al2O3 by atomic layer deposition (ALD) (see the Methods section of the Supporting Information).40−43 The XRD pattern of Al2O3-coated H-LNMO does not contain additional peaks ascribable to Al2O3, thus suggesting the deposition of a thin and amorphous layer (Figure 3a).44 The presence of an Al2O3 layer was further confirmed by X-ray photoemission spectroscopy (XPS), where peaks characteristic of Al2O3 were observed in the Al 2p and 2s spectra at 75.9 and 120.8 eV, respectively (Figure 3b).45,46 Scanning transmission electron microscopy (STEM) highlighted a discrete change in the atomic array between the crystalline LNMO and an amorphous Al2O3 layer estimated to be about 1 nm thick after five cycles of ALD (Figure 3c). As the number of ALD cycles increased from two to eight, the thickness of Al2O3 also increased from 0.4 to 1.4 nm, as confirmed by both STEM and ellipsometry (Figures S6 and S7).

Figure 3.

Figure 3

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Comparative (a) XRD patterns and (b) XPS survey spectra of H-LNMO and Al2O3-coated H-LNMO with five cycles of ALD. The inset shows a magnified view of the Al 2p region for the Al2O3-coated H-LNMO. (c) STEM images of Al2O3-coated H-LNMO after five ALD cycles. (d) GCD curves of SSBs with Al2O3-coated H-LNMO after five ALD cycles at a rate of 0.1 C. (e) EIS spectra of SSBs with Al2O3–H-LNMO and H-LNMO cathode composites after the first and 20th cycles.

To identify the optimal thickness of the Al2O3 coating layer, H-LNMO samples with Al2O3 surface layers deposited by a different number of ALD cycles (two, five, and eight cycles) were evaluated electrochemically. As shown in Figure S8a, the discharge capacity of H-LNMO increased from 83.4 to 99.4 mAh g–1 with two cycles of ALD. In addition, the initial Coulombic efficiency of H-LNMO with two ALD cycles improved to 81.4%, thus suggesting the mitigation of side reactions between LPSCl and coated LNMO at high operating potentials. Al2O3-coated H-LNMO with five ALD cycles exhibited an electrochemical performance similar to that of H-LNMO with two ALD cycles (Figure 3d). However, a comparison of the cycling performance between these two samples after 40 cycles revealed that the capacity retention of H-LNMO with fve ALD cycles was 62.1%, significantly higher than that of H-LNMO with two ALD cycles (53.7%) (Figure S8b).

As previously reported in a separate study, a coating layer combined synergistically with a hollow structure can effectively mitigate the volume change of the cathode material, and the constraint becomes increasingly significant as the thickness of the surface layer increases.18 Therefore, we speculate that the lower volume change of H-LNMO brought about by 1 nm of ALD-coated Al2O3 provides for improved capacity retention compared with thinner coating layers. Nonetheless, when the number of ALD cycles increased to eight, the capacity decreased to 91.1 mAh g–1, as the insufficient Li-conductivity of the Al2O3 layer hinders Li-ion migration (Figure S8a). In summary, 1 nm of Al2O3 deposited using five cycles of ALD provided the best compromise between cycling stability and discharge capacity in this study, and we therefore focused the rest of the investigation on this system (denoted as Al2O3–H-LNMO). Plasma FIB cross-section SEM images of the PC-LNMO composite cathode exhibited contact loss between PC-LNMO and LPSCl after a few cycles, whereas the Al2O3–H-LNMO composite cathode maintained intimate interfacial contact between Al2O3–H-LNMO and LPSCl after 100 cycles, thus confirming that the hollow microstructure coupled with Al2O3 layer effectively mitigates the volume change of the LNMO cathode (Figures S9 and S10).

XPS measurements of H-LNMO and Al2O3–H-LNMO composite cathodes were performed to identify the influence of the Al2O3 coating layer on decomposition processes. The presence of oxygenated sulfur and phosphorus compounds such as sulfites and phosphates, which result from the reaction between LNMO and LPSCl, was confirmed by the XPS analysis of the H-LNMO composite cathode after 50 cycles, whereas these compounds were barely detected in the Al2O3–H-LNMO composite cathode (Figure S11).47,48 This reveals that the Al2O3 surface layer effectively suppresses the interfacial reaction between LPSCl and H-LNMO, thus leading to the enhanced cycling performance of Al2O3–H-LNMO.

Electrochemical impedance spectroscopy (EIS) spectra of H-LNMO/LPSCl/Li–In and Al2O3–H-LNMO/LPSCl/Li–In are shown in Figure 3e. It was not possible to deconvolute the contributions of the cathode and the anode to the reaction resistance, as previously reported.22 Therefore, an equivalent circuit model combining the contributions from both the anode and the cathode into one reaction resistance, RE (where E stands for electrodes) was used to interpret the EIS spectra. The difference in resistance observed between the H-LNMO/LPSCl/Li–In and Al2O3–H-LNMO/LPSCl/Li–In systems can be directly attributed to the effect of the Al2O3 layer, as the anode is identical across both samples. The RE values of the coated and noncoated H-LNMO samples were 0.57 and 0.96 kΩ cm2, respectively, after the first discharge (Figure S12 and Table S1). After 20 cycles, the increase in resistance was more significant for the H-LNMO system than for the Al2O3–H-LNMO system, highlighting the efficacy of the protective layer in terms of stabilizing the cathode–SE interface at high potentials. The effect of the active material fraction in the composite cathode was explored by comparing Al2O3–H-LNMO/LPSCl/VCF compositions with material ratios of 40:55:5 and 70:25:5. Although high cathode fractions naturally lower the fraction of solid electrolyte and increase the tortuosity of ionic paths, both composite cathodes delivered similar capacities of 94.9  (70 wt %) and 99.4 mAh g–1 (40 wt %), which confirms the facile Li-ion diffusion in H-LNMO (Figure S13).

To demonstrate the benefits of H-LNMO in a realistic cathode configuration, a film-type composite cathode was fabricated using a polytetrafluoroethylene (PTFE)-based dry processing method49 (Figure S14). The fibrous network produced by PTFE under the shear stress of repeated grinding steps forms a cohesive composite cathode with good ionic and electronic transport.50,51 The GCD curves of Al2O3–H-LNMO/LPSCl/Li–In with pellet- and film-type composite cathodes are displayed in Figure 4a and b, respectively. The cells were cycled under constant current–constant voltage (CC–CV) charge and CC discharge to promote the full delithiation of the H-LNMO lattice. The first discharge capacities were 105.5 and 89.8 mAh g–1 for the pellet- and film-type cathodes, respectively, at a C-rate of 0.1 C. After 100 cycles, the capacity retention of the cells cycled with the pellet- and film-type composite cathodes were 62.1% and 70.1%, respectively; thus, both cathodes displayed stable cycling performance even with a high active material loading (14 and 27 mg cm–2 for pellet- and film-type composite cathodes, respectively) (Figure 4c). The enhanced capacity retention of the film-type composite cathode can be attributed to the ability of the PTFE fibrils to maintain the contact between LPSCl, Al2O3–H-LNMO, and VCF upon cycling. The areal capacities of pellet- and film-type composite cathodes were 1.51 and 2.46 mAh cm–2, respectively, which were 7–10× higher than those of previously reported SSBs composed of LNMO and a sulfide electrolyte,22,23,52−56 thus confirming the importance of microstructure engineering cathode secondary particles to achieve high areal capacities and long-term cyclability in SSBs (Figure 4d and e and Table S2).

Figure 4.

Figure 4

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Comparative GCD curves of Al2O3–H-LNMO/LPSCl/Li–In cells with (a) pellet- and (b) film-type composite cathodes (70:25:5) at a rate of 0.1 C under the CC–CV mode. (c) Cycling performance of SSBs with pellet- and film-type Al2O3–H-LNMO composite cathodes. The rate was increased to 0.2 C after the first three cycles, which were performed at a rate of 0.1 C. Comparison of (d) the initial areal and specific capacities and (e) the capacity retention of SSBs composed of LNMO and solid sulfide electrolytes between this study and reference data.

In conclusion, we have demonstrated that a hollow microstructure coupled with a stable surface layer significantly improves both the cycling performance and the rate capability of LNMO-based cathodes with a high active material loading. The hollow microstructure reduces the Li-ion diffusion path, leading to lower overpotentials and faster reaction kinetics at the electrode surface. The hollow secondary particle morphology coupled with the Al2O3 surface coating effectively mitigates both the volume change and the induced stress level in LNMO during lithium insertion and extraction, minimizing contact loss between the cathode and the solid electrolyte and resulting in improved cycling stability. This study highlights the importance of cathode microstructure engineering in SSBs and provides design strategies that can be extended to more traditional cathode chemistries.

Acknowledgments

The authors would like to acknowledge the ISCF Faraday Challenge project SOLBAT (Grant FIRG026) and the Henry Royce Institute (through UK Engineering and Physical Science Research Council Grant EP/R010145/1) for capital equipment. We acknowledge technical support of the 7D beamline at the Pohang Accelerator Laboratory (PAL). H.J. Lee acknowledges support from the National Research Foundation of Korea (NRF2019R1A6A3A03031343). X. Liu acknowledges support from KC Wong Education Foundation from Hong Kong. We are grateful to the David Cockayne Centre for Electron Microscopy for the use of their electron microscopes.

Supporting Information Available

The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acs.nanolett.2c02426.

  • Details on materials and methods, PSD curves of H-LNMO and PC-LNMO, EIS spectra and Arrhenius plot of LPSCl, SEM images of PC-LNMO, STEM images of Al2O3-coated H-LNMO after ALD cycles, and GCD curves of H-LNMO with an Al2O3 layer formed under a different number of ALD cycles (PDF)

Author Contributions

H. J. Lee and X. Liu contributed equally.

The authors declare no competing financial interest.

Supplementary Material

nl2c02426_si_001.pdf (2.5MB, pdf)

References

  1. Manthiram A.; Yu X.; Wang S. Lithium battery chemistries enabled by solid-state electrolytes. Nat. Rev. Mater. 2017, 2, 16103. 10.1038/natrevmats.2016.103. [DOI] [Google Scholar]
  2. Lau J.; DeBlock R. H.; Butts D. M.; Ashby D. S.; Choi C. S.; Dunn B. S. Sulfide solid electrolytes for lithium battery applications. Adv. Energy Mater. 2018, 8, 1800933. 10.1002/aenm.201800933. [DOI] [Google Scholar]
  3. Sakuda A.; Hayashi A.; Tatsumisago M. Recent progress on interface formation in all-solid-state batteries. Current Opinion in Electrochemistry 2017, 6, 108–114. 10.1016/j.coelec.2017.10.008. [DOI] [Google Scholar]
  4. Hikima K.; Totani M.; Obokata S.; Muto H.; Matsuda A. Mechanical Properties of Sulfide-Type Solid Electrolytes Analyzed by Indentation Methods. ACS Applied Energy Materials 2022, 5, 2349–2355. 10.1021/acsaem.1c03829. [DOI] [Google Scholar]
  5. Lian P.-J.; Zhao B.-S.; Zhang L.-Q.; Xu N.; Wu M.-T.; Gao X.-P. Inorganic sulfide solid electrolytes for all-solid-state lithium secondary batteries. Journal of Materials Chemistry A 2019, 7, 20540–20557. 10.1039/C9TA04555D. [DOI] [Google Scholar]
  6. Albertus P.; Anandan V.; Ban C.; Balsara N.; Belharouak I.; Buettner-Garrett J.; Chen Z.; Daniel C.; Doeff M.; Dudney N. J.; et al. Challenges for and pathways toward Li-metal-based all-solid-state batteries. ACS Energy Letters 2021, 6, 1399–1404. 10.1021/acsenergylett.1c00445. [DOI] [Google Scholar]
  7. Wu C.; Lou J.; Zhang J.; Chen Z.; Kakar A.; Emley B.; Ai Q.; Guo H.; Liang Y.; Lou J.; et al. Current status and future directions of all-solid-state batteries with lithium metal anodes, sulfide electrolytes, and layered transition metal oxide cathodes. Nano Energy 2021, 87, 106081. 10.1016/j.nanoen.2021.106081. [DOI] [Google Scholar]
  8. Liu X.; Zheng B.; Zhao J.; Zhao W.; Liang Z.; Su Y.; Xie C.; Zhou K.; Xiang Y.; Zhu J.; et al. Electrochemo-Mechanical Effects on Structural Integrity of Ni-Rich Cathodes with Different Microstructures in All Solid-State Batteries. Adv. Energy Mater. 2021, 11, 2003583. 10.1002/aenm.202003583. [DOI] [Google Scholar]
  9. Koerver R.; Aygün I.; Leichtweiß T.; Dietrich C.; Zhang W.; Binder J. O.; Hartmann P.; Zeier W. G.; Janek J. Capacity fade in solid-state batteries: Interphase formation and chemomechanical processes in nickel-rich layered oxide cathodes and lithium thiophosphate solid electrolytes. Chem. Mater. 2017, 29, 5574–5582. 10.1021/acs.chemmater.7b00931. [DOI] [Google Scholar]
  10. Shearing P. R. Batteries: Imaging degradation. Nature Energy 2016, 1, 16173. 10.1038/nenergy.2016.173. [DOI] [Google Scholar]
  11. Mao Y.; Wang X.; Xia S.; Zhang K.; Wei C.; Bak S.; Shadike Z.; Liu X.; Yang Y.; Xu R.; et al. High-voltage charging-induced strain, heterogeneity, and micro-cracks in secondary particles of a nickel-rich layered cathode material. Adv. Funct. Mater. 2019, 29, 1900247. 10.1002/adfm.201900247. [DOI] [Google Scholar]
  12. Ruess R.; Schweidler S.; Hemmelmann H.; Conforto G.; Bielefeld A.; Weber D. A.; Sann J.; Elm M. T.; Janek J. Influence of NCM particle cracking on kinetics of lithium-ion batteries with liquid or solid electrolyte. J. Electrochem. Soc. 2020, 167, 100532. 10.1149/1945-7111/ab9a2c. [DOI] [Google Scholar]
  13. Trevisanello E.; Ruess R.; Conforto G.; Richter F. H.; Janek J. Polycrystalline and single crystalline NCM cathode materials—quantifying particle cracking, active surface area, and lithium diffusion. Adv. Energy Mater. 2021, 11, 2003400. 10.1002/aenm.202003400. [DOI] [Google Scholar]
  14. de Biasi L.; Lieser G.; Dräger C.; Indris S.; Rana J.; Schumacher G.; Mönig R.; Ehrenberg H.; Binder J. R.; Geßwein H. LiCaFeF6: A zero-strain cathode material for use in Li-ion batteries. J. Power Sources 2017, 362, 192–201. 10.1016/j.jpowsour.2017.07.007. [DOI] [Google Scholar]
  15. Lee E.; Kwon B. J.; Dogan F.; Ren Y.; Croy J. R.; Thackeray M. M. Lithiated Spinel LiCo1–x Al x O2 as a Stable Zero-Strain Cathode. ACS Applied Energy Materials 2019, 2, 6170–6175. 10.1021/acsaem.9b01503. [DOI] [Google Scholar]
  16. Wang X.; Xiao R.; Li H.; Chen L. Quantitative structure-property relationship study of cathode volume changes in lithium ion batteries using ab-initio and partial least squares analysis. Journal of Materiomics 2017, 3, 178–183. 10.1016/j.jmat.2017.02.002. [DOI] [Google Scholar]
  17. Strauss F.; de Biasi L.; Kim A.-Y.; Hertle J.; Schweidler S.; Janek J.; Hartmann P.; Brezesinski T. Rational design of quasi-zero-strain NCM cathode materials for minimizing volume change effects in all-solid-state batteries. ACS Materials Letters 2020, 2, 84–88. 10.1021/acsmaterialslett.9b00441. [DOI] [Google Scholar]
  18. Lee H. J.; Brown Z.; Zhao Y.; Fawdon J.; Song W.; Lee J. H.; Ihli J.; Pasta M. Ordered LiNi0. 5Mn1. 5O4 Cathode in Bis (fluorosulfonyl) imide-Based Ionic Liquid Electrolyte: Importance of the Cathode–Electrolyte Interphase. Chem. Mater. 2021, 33, 1238–1248. 10.1021/acs.chemmater.0c04014. [DOI] [Google Scholar]
  19. Li W.; Cho Y.-G.; Yao W.; Li Y.; Cronk A.; Shimizu R.; Schroeder M. A.; Fu Y.; Zou F.; Battaglia V.; et al. Enabling high areal capacity for Co-free high voltage spinel materials in next-generation Li-ion batteries. J. Power Sources 2020, 473, 228579. 10.1016/j.jpowsour.2020.228579. [DOI] [Google Scholar]
  20. Zou Z.; Xu H.; Zhang H.; Tang Y.; Cui G. Electrolyte Therapy for Improving the Performance of LiNi0. 5Mn1. 5O4 Cathodes Assembled Lithium–Ion Batteries. ACS Appl. Mater. Interfaces 2020, 12, 21368–21385. 10.1021/acsami.0c02516. [DOI] [PubMed] [Google Scholar]
  21. Zhang W.; Richter F. H.; Culver S. P.; Leichtweiss T.; Lozano J. G.; Dietrich C.; Bruce P. G.; Zeier W. G.; Janek J. Degradation mechanisms at the Li10GeP2S12/LiCoO2 cathode interface in an all-solid-state lithium-ion battery. ACS Appl. Mater. Interfaces 2018, 10, 22226–22236. 10.1021/acsami.8b05132. [DOI] [PubMed] [Google Scholar]
  22. Oh G.; Hirayama M.; Kwon O.; Suzuki K.; Kanno R. Bulk-type all solid-state batteries with 5 V class LiNi0. 5Mn1. 5O4 cathode and Li10GeP2S12 solid electrolyte. Chem. Mater. 2016, 28, 2634–2640. 10.1021/acs.chemmater.5b04940. [DOI] [Google Scholar]
  23. Liu G.; Lu Y.; Wan H.; Weng W.; Cai L.; Li Z.; Que X.; Liu H.; Yao X. Passivation of the Cathode–Electrolyte Interface for 5 V-Class All-Solid-State Batteries. ACS Appl. Mater. Interfaces 2020, 12, 28083–28090. 10.1021/acsami.0c03610. [DOI] [PubMed] [Google Scholar]
  24. Kondrakov A. O.; Schmidt A.; Xu J.; Geßwein H.; Mönig R.; Hartmann P.; Sommer H.; Brezesinski T.; Janek J. Anisotropic lattice strain and mechanical degradation of high-and low-nickel NCM cathode materials for Li-ion batteries. J. Phys. Chem. C 2017, 121, 3286–3294. 10.1021/acs.jpcc.6b12885. [DOI] [Google Scholar]
  25. Lim J.-M.; Hwang T.; Kim D.; Park M.-S.; Cho K.; Cho M. Intrinsic origins of crack generation in Ni-rich LiNi0. 8Co0. 1Mn0. 1O2 layered oxide cathode material. Sci. Rep. 2017, 7, 39669. 10.1038/srep39669. [DOI] [PMC free article] [PubMed] [Google Scholar]
  26. Zheng J.; Xiao J.; Yu X.; Kovarik L.; Gu M.; Omenya F.; Chen X.; Yang X.-Q.; Liu J.; Graff G. L.; et al. Enhanced Li+ ion transport in LiNi 0.5 Mn 1.5 O 4 through control of site disorder. Physical chemistry chemical physics 2012, 14, 13515–13521. 10.1039/c2cp43007j. [DOI] [PubMed] [Google Scholar]
  27. Li W.; Asl H. Y.; Xie Q.; Manthiram A. Collapse of LiNi1–x–y Co x Mn y O2 Lattice at Deep Charge Irrespective of Nickel Content in Lithium-Ion Batteries. Journal of the American chemical society 2019, 141, 5097–5101. 10.1021/jacs.8b13798. [DOI] [PubMed] [Google Scholar]
  28. Papakyriakou M.; Lu M.; Liu Y.; Liu Z.; Chen H.; McDowell M. T.; Xia S. Mechanical behavior of inorganic lithium-conducting solid electrolytes. J. Power Sources 2021, 516, 230672. 10.1016/j.jpowsour.2021.230672. [DOI] [Google Scholar]
  29. Chen S.; Xie D.; Liu G.; Mwizerwa J. P.; Zhang Q.; Zhao Y.; Xu X.; Yao X. Sulfide solid electrolytes for all-solid-state lithium batteries: structure, conductivity, stability and application. Energy Storage Materials 2018, 14, 58–74. 10.1016/j.ensm.2018.02.020. [DOI] [Google Scholar]
  30. Zhao F.; Liang J.; Yu C.; Sun Q.; Li X.; Adair K.; Wang C.; Zhao Y.; Zhang S.; Li W.; et al. A versatile Sn-substituted argyrodite sulfide electrolyte for all-solid-state Li metal batteries. Adv. Energy Mater. 2020, 10, 1903422. 10.1002/aenm.201903422. [DOI] [Google Scholar]
  31. Santhosha A.; Medenbach L.; Buchheim J. R.; Adelhelm P. The indium- lithium electrode in solid-state lithium-ion batteries: phase formation, redox potentials, and interface stability. Batteries & Supercaps 2019, 2, 524–529. 10.1002/batt.201800149. [DOI] [Google Scholar]
  32. Allen J. M.; Weddle P. J.; Verma A.; Mallarapu A.; Usseglio-Viretta F.; Finegan D. P.; Colclasure A. M.; Mai W.; Schmidt V.; Furat O.; et al. Quantifying the influence of charge rate and cathode-particle architectures on degradation of Li-ion cells through 3D continuum-level damage models. J. Power Sources 2021, 512, 230415. 10.1016/j.jpowsour.2021.230415. [DOI] [Google Scholar]
  33. Manthiram A.; Chemelewski K.; Lee E.-S. A perspective on the high-voltage LiMn 1.5 Ni 0.5 O 4 spinel cathode for lithium-ion batteries. Energy Environ. Sci. 2014, 7, 1339–1350. 10.1039/c3ee42981d. [DOI] [Google Scholar]
  34. Liu D.; Zhu W.; Trottier J.; Gagnon C.; Barray F.; Guerfi A.; Mauger A.; Groult H.; Julien C.; Goodenough J.; et al. Spinel materials for high-voltage cathodes in Li-ion batteries. Rsc Advances 2014, 4, 154–167. 10.1039/C3RA45706K. [DOI] [Google Scholar]
  35. Kim J.-H.; Huq A.; Chi M.; Pieczonka N. P.; Lee E.; Bridges C. A.; Tessema M. M.; Manthiram A.; Persson K. A.; Powell B. R. Integrated nano-domains of disordered and ordered spinel phases in LiNi0. 5Mn1. 5O4 for Li-ion batteries. Chem. Mater. 2014, 26, 4377–4386. 10.1021/cm501203r. [DOI] [Google Scholar]
  36. Yang J.; Han X.; Zhang X.; Cheng F.; Chen J. Spinel LiNi0. 5Mn1. 5O4 cathode for rechargeable lithiumion batteries: Nano vs micro, ordered phase (P4332) vs disordered phase (Fd–3̅m. Nano Research 2013, 6, 679–687. 10.1007/s12274-013-0343-5. [DOI] [Google Scholar]
  37. Yoon K.; Kim J.-J.; Seong W. M.; Lee M. H.; Kang K. Investigation on the interface between Li10GeP2S12 electrolyte and carbon conductive agents in all-solid-state lithium battery. Sci. Rep. 2018, 8, 8066. 10.1038/s41598-018-26101-4. [DOI] [PMC free article] [PubMed] [Google Scholar]
  38. Schwietert T. K.; Arszelewska V. A.; Wang C.; Yu C.; Vasileiadis A.; de Klerk N. J.; Hageman J.; Hupfer T.; Kerkamm I.; Xu Y.; et al. Clarifying the relationship between redox activity and electrochemical stability in solid electrolytes. Nature materials 2020, 19, 428–435. 10.1038/s41563-019-0576-0. [DOI] [PubMed] [Google Scholar]
  39. Strauss F.; Bartsch T.; de Biasi L.; Kim A.-Y.; Janek J.; Hartmann P.; Brezesinski T. Impact of cathode material particle size on the capacity of bulk-type all-solid-state batteries. ACS Energy Letters 2018, 3, 992–996. 10.1021/acsenergylett.8b00275. [DOI] [Google Scholar]
  40. Banerjee A.; Tang H.; Wang X.; Cheng J.-H.; Nguyen H.; Zhang M.; Tan D. H.; Wynn T. A.; Wu E. A.; Doux J.-M.; et al. Revealing nanoscale solid–solid interfacial phenomena for long-life and high-energy all-solid-state batteries. ACS Appl. Mater. Interfaces 2019, 11, 43138–43145. 10.1021/acsami.9b13955. [DOI] [PubMed] [Google Scholar]
  41. Negi R. S.; Yusim Y.; Pan R.; Ahmed S.; Volz K.; Takata R.; Schmidt F.; Henss A.; Elm M. T. A Dry-Processed Al2O3/LiAlO2 Coating for Stabilizing the Cathode/Electrolyte Interface in High-Ni NCM-Based All-Solid-State Batteries. Advanced Materials Interfaces 2022, 9, 2101428. 10.1002/admi.202101428. [DOI] [Google Scholar]
  42. Dong M.; Wang Z.; Li H.; Guo H.; Li X.; Shih K.; Wang J. Metallurgy inspired formation of homogeneous Al2O3 coating layer to improve the electrochemical properties of LiNi0. 8Co0. 1Mn0. 1O2 cathode material. ACS Sustainable Chem. Eng. 2017, 5, 10199–10205. 10.1021/acssuschemeng.7b02178. [DOI] [Google Scholar]
  43. Zhang X.; Belharouak I.; Li L.; Lei Y.; Elam J. W.; Nie A.; Chen X.; Yassar R. S.; Axelbaum R. L. Structural and electrochemical study of Al2O3 and TiO2 coated Li1. 2Ni0. 13Mn0. 54Co0. 13O2 cathode material using ALD. Adv. Energy Mater. 2013, 3, 1299–1307. 10.1002/aenm.201300269. [DOI] [Google Scholar]
  44. Negi R. S.; Culver S. P.; Mazilkin A.; Brezesinski T.; Elm M. T. Enhancing the electrochemical performance of LiNi0. 70Co0. 15Mn0. 15O2 cathodes using a practical solution-based Al2O3 coating. ACS Appl. Mater. Interfaces 2020, 12, 31392–31400. 10.1021/acsami.0c06484. [DOI] [PubMed] [Google Scholar]
  45. Iatsunskyi I.; Kempiński M.; Jancelewicz M.; Załęski K.; Jurga S.; Smyntyna V. Structural and XPS characterization of ALD Al2O3 coated porous silicon. Vacuum 2015, 113, 52–58. 10.1016/j.vacuum.2014.12.015. [DOI] [Google Scholar]
  46. Guan D.; Jeevarajan J. A.; Wang Y. Enhanced cycleability of LiMn2O4 cathodes by atomic layer deposition of nanosized-thin Al2O3 coatings. Nanoscale 2011, 3, 1465–1469. 10.1039/c0nr00939c. [DOI] [PubMed] [Google Scholar]
  47. Walther F.; Strauss F.; Wu X.; Mogwitz B.; Hertle J.; Sann J.; Rohnke M.; Brezesinski T.; Janek J. The working principle of a Li2CO3/LiNbO3 coating on NCM for thiophosphate-based all-solid-state batteries. Chem. Mater. 2021, 33, 2110–2125. 10.1021/acs.chemmater.0c04660. [DOI] [Google Scholar]
  48. Auvergniot J.; Cassel A.; Ledeuil J.-B.; Viallet V.; Seznec V.; Dedryvère R. Interface stability of argyrodite Li6PS5Cl toward LiCoO2, LiNi1/3Co1/3Mn1/3O2, and LiMn2O4 in bulk all-solid-state batteries. Chem. Mater. 2017, 29, 3883–3890. 10.1021/acs.chemmater.6b04990. [DOI] [Google Scholar]
  49. Xu L.; Lu Y.; Zhao C.-Z.; Yuan H.; Zhu G.-L.; Hou L.-P.; Zhang Q.; Huang J.-Q. Toward the Scale-Up of Solid-State Lithium Metal Batteries: The Gaps between Lab-Level Cells and Practical Large-Format Batteries. Adv. Energy Mater. 2021, 11, 2002360. 10.1002/aenm.202002360. [DOI] [Google Scholar]
  50. Jiang T.; He P.; Wang G.; Shen Y.; Nan C.-W.; Fan L.-Z. Solvent-Free Synthesis of Thin, Flexible, Nonflammable Garnet-Based Composite Solid Electrolyte for All-Solid-State Lithium Batteries. Adv. Energy Mater. 2020, 10, 1903376. 10.1002/aenm.201903376. [DOI] [Google Scholar]
  51. Lu Y.; Zhao C.-Z.; Yuan H.; Hu J.-K.; Huang J.-Q.; Zhang Q. Dry electrode technology, the rising star in solid-state battery industrialization. Matter 2022, 5, 876–898. 10.1016/j.matt.2022.01.011. [DOI] [Google Scholar]
  52. Li J.; Ma C.; Chi M.; Liang C.; Dudney N. J. Solid electrolyte: the key for high-voltage lithium batteries. Adv. Energy Mater. 2015, 5, 1401408. 10.1002/aenm.201401408. [DOI] [Google Scholar]
  53. Yubuchi S.; Ito Y.; Matsuyama T.; Hayashi A.; Tatsumisago M. 5 V class LiNi0. 5Mn1. 5O4 positive electrode coated with Li3PO4 thin film for all-solid-state batteries using sulfide solid electrolyte. Solid State Ionics 2016, 285, 79–82. 10.1016/j.ssi.2015.08.001. [DOI] [Google Scholar]
  54. Wang Y.; Lv Y.; Su Y.; Chen L.; Li H.; Wu F. 5V-class sulfurized spinel cathode stable in sulfide all-solid-state batteries. Nano Energy 2021, 90, 106589. 10.1016/j.nanoen.2021.106589. [DOI] [Google Scholar]
  55. Lee S.; Kim H.; Lee J.-H.; Kim B.-K.; Shin H.; Kim J.; Park S. Nano-interface engineering in all-solid-state lithium metal batteries: Tailoring exposed crystal facets of epitaxially grown LiNi0. 5Mn1. 5O4 films. Nano Energy 2021, 79, 105480. 10.1016/j.nanoen.2020.105480. [DOI] [Google Scholar]
  56. Jang J.; Chen Y.-T.; Deysher G.; Cheng D.; Ham S.-Y.; Cronk A.; Ridley P.; Yang H.; Sayahpour B.; Han B.; et al. Enabling a Co-Free, High-Voltage LiNi0. 5Mn1. 5O4 Cathode in All-Solid-State Batteries with a Halide Electrolyte. ACS Energy Letters 2022, 7, 2531–2539. 10.1021/acsenergylett.2c01397. [DOI] [Google Scholar]

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