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The lithium–air battery has great potential of achieving specific energy density comparable to that of gasoline. Several lithium oxide phases involved in the charge–discharge process greatly affect the overall performance of lithium–air batteries. One of the key issues is linked to the environmental oxygen‐rich conditions during battery cycling. Here, the theoretical prediction and experimental confirmation of new stable oxygen‐rich lithium oxides under high pressure conditions are reported. Three new high pressure oxide phases that form at high temperature and pressure are identified: Li2O3, LiO2, and LiO4. The LiO2 and LiO4 consist of a lithium layer sandwiched by an oxygen ring structure inherited from high pressure ε‐O8 phase, while Li2O3 inherits the local arrangements from ambient LiO2 and Li2O2 phases. These novel lithium oxides beyond the ambient Li2O, Li2O2, and LiO2 phases show great potential in improving battery design and performance in large battery applications under extreme conditions.
Lithium‐ion batteries can store a large amount of energy in a relatively small volume and have been extensively used as rechargeable batteries for portable electronics. Over the last decade, lithium–air (Li–O2) batteries have attracted great attention on new battery development as they have a gravimetric energy density close to that of gasoline.1, 2, 3, 4 Li–O2 batteries use the oxidation of lithium at the anode and the reduction of oxygen at the cathode to create a current. It is commonly known that the Li–O2 battery often forms insoluble discharge products, mainly oxides, which accelerate the degradation of the electrode and electrolyte, thus reducing the cycle stability and efficiency.5, 6, 7, 8, 9, 10, 11 Recently, novel approaches to combat this degradation have been actively pursued by forming LiOH12 or stable LiO2.13 By analogy to sodium14 and potassium15 superoxide, lithium superoxide has been considered as an alternative cathode based on reduced graphene oxide.13 The major problem is that the lithium superoxide is not stable at ambient condition. Investigation of the stability of these known phases and new forms of lithium oxides would greatly extend our knowledge on improving the capability and lifetime of lithium–air batteries.
There have been some studies on the lithium oxides at various conditions. Yao et al. investigated the thermal stabilities of Li2O2 and Li2O at the battery working temperature.5 Shi et al. reported density functional theory (DFT) calculations and experimental confirmation of Li3O4 nanoparticles as a discharge byproduct.6 Also, the recent discovery of lithium superoxide as a discharge product has attracted much attention, and it is considered as a highly promising candidate for the next‐generation lithium battery.7, 8, 9, 10, 11, 13
Pressure as an efficient way to tune the lattice and electronic structure has been extensively used to explore novel material synthesis. Sodium chloride displays the polymorphisms Na3Cl and NaCl3 under pressure.16 The newly discovered stable phases magnesium and iron peroxides (MgO2 and FeO2) formed from a high pressure and temperature redox reaction provide a new look at oxygen and hydrogen cycling in the deep earth interior.17, 18 Ultrahigh pressure sulfur hydride demonstrates superconducting behavior at record high temperature, 203 K.19 We addressed two questions. What is the stability of the aforementioned lithium oxides under high pressure? Can we synthesize even higher oxygen content lithium oxides by application of pressure? In particular, we investigated the structural stability of pure Li2O2 and mixture of Li2O2 with oxygen at high pressure, and found that the pure Li2O2 is robustly stable up to 57 GPa, while the mixture of Li2O2 with adequate oxygen environment produces a series of oxygen‐rich phases under high pressure and temperature. We also applied DFT calculations to search the possible thermodynamically stable phases, and found that the calculated results matched the experimental observations. This may inspire broader applications of these new forms of lithium oxides.
At ambient condition, both lithium oxide (Li2O) and lithium peroxide (Li2O2) are thermodynamically stable. During the charge–discharge cycling of Li–O2 batteries, Li2O2 plays the major role. It has been reported that a small amount of lithium superoxide (LiO2) nanoparticles can form on the surface of the Li2O2.7, 8, 9, 13 To check the stability and possible formation of high‐pressure oxygen‐rich lithium oxides, we started with pure Li2O2 (Sigma‐Aldrich) powder loaded in a diamond anvil cell without any pressure‐transmitting medium for a test at high pressure and room temperature. The Li2O2 powder was compressed to 57 GPa and subjected to synchrotron X‐ray diffraction (XRD) to follow the structural evolution as a function of pressure. Figure 1 a shows the angle‐dispersive XRD profiles for the powder at various pressures. All diffraction peaks shift to higher 2θ as pressure is increased. Up to the highest pressure measured, no symmetry change was observed. The XRD patterns can be described by the ambient P63/mmc symmetry to the highest pressure. As shown in Figure Figure1b,1b, the compression curve (unit cell volume vs pressure) can be fit to the third‐order Birch–Murnaghan equation of state with bulk modulus B o = 94.77 GPa and derivative of B o as 3.41.
High‐pressure XRD measurements of Li2O2 up to 57 GPa show the robustly stable phase P63/mmc at room temperature. a) The XRD profiles at various pressures up to 57 GPa. b) Unit cell volume versus pressure. The dashed line presents the fitting result ...
On the second run, Li2O2 powder was loaded with cryogenically condensed liquid oxygen in the sample chamber of a diamond anvil cell. The mixture of Li2O2 powder and liquid oxygen was precompressed to 15.0 GPa, followed by heating to 2200 K at high pressure using a Nd:YAG laser system. After the laser heating, the pressure in the sample chamber dropped to 14.4 GPa. As the Li2O2 powder is semitransparent and no thermal shielding layers were used to prevent heat from conducting away from the diamond anvils, a high laser power (total 80 W from a double‐side laser heating unit) was needed to heat the sample to the maximum temperature of 2200 K. A 2D raster scan was performed around the laser‐processed center of the sample, and the powder diffraction pattern was collected at each scanning location. We clearly saw totally different diffraction profiles in the laser‐processed center area, with the most diffraction peaks being spotty, indicating new structures had been synthesized in the form of many small single‐crystal grains. In the diffraction profile of the central 20 µm region where the laser heating was applied, one broad smooth powder ring appeared near 2θ = 7.8°, which was not evident outside this region. Upon opening the diamond anvil cell, we realized that the central area of the anvil had been damaged by the high‐power laser beams (see Figure S1 in the Supporting Information), and part of the carbon had been removed from the diamond culet surface.
On the third run, the Li2O2 powder was sandwiched between two thin layers of LiF pellets, and loaded with liquid oxygen in a diamond anvil cell. The sample was compressed to 50.0 GPa, followed by laser heating. The pressure inside the chamber dropped to 48.0 GPa after cooling to room temperature. With the thermal insulator LiF layers, only 20 W power was needed to heat the sample above 2000 K, and no damage was observed on the diamond surfaces. Synchrotron X‐ray diffraction was taken at the laser‐processed location. The diffraction profile changed dramatically from the previous two runs, indicating that new structures had been synthesized.
To clarify the high temperature requirement for synthesizing these new phases from previous three runs, we conducted one more room temperature compression experiment in a diamond anvil cell. Mixture of Li2O2 powder and oxygen was compressed to 53 GPa without laser heating. The selected XRD patterns around 15 and 50 GPa are shown in Figure S2 (Supporting Information). All diffraction peaks can be characterized by the known ambient pressure Li2O2 phase (P63/mmc) and oxygen ε‐O8 phase (C2/m, a stable high pressure phase with pressure greater than 10 GPa) up to the highest pressure in this run.
Crystal structure searching based on DFT was conducted to understand the energy landscape of the Li–O compounds in the experimental environments. With two end members, Li2O2 and O2, we predicted possible stoichiometry and crystal structure at 15 and 48 GPa, as shown in Figure 2 . At 15 GPa, we found that Li2O3, LiO2, and LiO4 are stable phases, with LiO2 and LiO4 remaining stable even at 48 GPa. At 15 GPa, Li2O3 and LiO4 have Im‐3m and Ibam space groups, respectively. It is interesting to see that for LiO2, the transition pressure from the known ambient Pnnm phase to the new P4/mbm phase is at 12 GPa, close to our second run experimental condition around 15 GPa. The enthalpy plot of LiO2 is shown in Figure S3 (Supporting Information). The formation enthalpy of stable phases with respect to decomposition into Li2O2 and O2 is less than 0.1 eV per atom, and some phases possess total energy close to that of the stable phases. Thus, it is likely that the temperature effect could play a role in the thermodynamic stability.
The predicted convex hulls of Li–O at a) 14.4 GPa and b) 48 GPa. To check the thermostability, the temperature effect has been considered from 0 to 1000 K. At 48 GPa, the phonon stability of LiO2 (P4/mbm) decreases as the temperature increases, ...
To understand the thermodynamic stability of each phase, we conducted phonon calculations. Clearly, these candidate phases show stable phonon dispersion relations (see Figure S4 in the Supporting Information). To compare the synthesizing condition with high temperature, we also tested the temperature effect up to 1000 K on the formation enthalpy at 48 GPa, using a quasiharmonic approximation. While other phases remain almost constant, LiO2 shows a tendency to become less stable at higher temperature.
Bader charge analysis provided further insight into the bonding nature between Li and O2 units. The effective charges on the Li/O2 unit in Li2O2 are +1.6 and −1.6, and the O—O bonding distance is 1.50 Å, compared to 1.21 Å in the solid oxygen. By taking more oxygen, the effective charge of the O2 unit is reduced to −1.07 (Li2O3), −0.82 (LiO2), and −0.41 (LiO4), forming superoxides. The corresponding bond length of O2 changes to 1.36, 1.31, and 1.25 Å, respectively, which are close to that of solid oxygen. The effective charge of Li remains almost constant and occupies similar volumes in all Li–O compounds. Therefore, we speculate that Li–O compounds under pressure take advantage of having smaller molecular volume of oxygen units by reducing electrons at antibonding states. In other words, Li–O compounds tend to form superoxides under pressure to lower the total energy by reducing their O2 volume. This trend can be also observed in the phonon dispersions curves (see Figure S4 in the Supporting Information). The calculated phonon dispersion of Li2O2 at 48 GPa was stable, a finding in good agreement with our pure Li2O2 high pressure experiments. Increasing oxygen concentrations in oxygen‐rich phases show higher vibrational modes of O2 units, and we can see that the O2 phonon band splits from the lower energy phonon bands.
For interpreting the 14.4 GPa XRD results, we considered that the carbon that escaped from the diamond anvil surface may participate in the new compound formation. The powder diffraction profile fit well with the Li4CO4 C1m1 phase predicted by Cancarevic et al.,20 as well as the LiO2 (Pnnm) and LiO2 (P4/mbm) phases from our DFT calculations. Figure 3 shows the unrolled XRD pattern at 14.4 GPa and the simulated diffractions from Li4CO4 (C1m1), LiO2 (Pnnm), and LiO2 (P4/mbm) phases. The distinguishing feature on the diffraction pattern is the very spotty diffraction rings, indicating micrometer‐sized grains with well‐annealed single crystals. The high temperature promotes the chemical reaction between Li2O2 and oxygen, and also allows the crystal growth of the new phases. The Bragg diffraction positions from these three phases match the d‐spacings from the powder diffraction. We conducted Reitveld refinement on the integrated 1D pattern with the above three phases. Although the intensity cannot be fitted very well due to the spotty patterns, the lattice parameters can be obtained with this refinement. Roughly, each phase occupies about 1/3 volumetrically. The fitting result and parameters of these three phases are displayed in Figure S5 and Table S1 (Supporting Information), respectively. With 14.4 GPa pressure and high temperature, the data indicate that the following redox reactions take place
High‐pressure XRD pattern after laser heating at 14.4 GPa. The cake view of the 2D diffraction pattern shows many sharp diffraction spots after laser heating, indicating new phases are present in the form of many small single crystals. The total ...
Thus, the new compounds Li4CO4 and LiO2 are formed with further reduction and oxidation from pristine Li2O2 by carbon and oxygen, respectively. Both Pnnm and P4/mbm LiO2 phases are present at this pressure, which is close to the DFT calculation result on the Pnnm→P4/mbm transition pressure near 12 GPa. Cancarevic et al. proposed that the Li4CO4 (C1m1) phase could be synthesized in the pressure range 80–110 GPa.21 Grzechnik et al. attempted to form Li4CO4 from a mixture of Li2O and Li2CO3 but failed to obtain the predicted Li4CO4 phase up to 25 GPa and 1100 K.20 Our diamond anvil test results show the successful synthesis of Li4CO4 from Li2O2 and vapor carbon at 14.4 GPa and 2200 K via a redox reaction, which provides a much lower pressure route to form lithium orthocarbonate. For comparison, we also took diffraction patterns at off‐center locations. In the bottom panel of Figure S5 (Supporting Information), the XRD profile taken at 30 µm away from the laser center is shown, where much lower heating temperature is expected. Very small amount of Li4CO4 was formed and some not well formed LiO2 P4/mbm and Pnnm phases (broad and low intensity peaks) were present, which indicates the temperature is an important parameter for the new LiO2 phase synthesis.
Because at 48 GPa, the XRD Debye–Scherrer rings are smooth, we obtained good powder diffraction patterns for structural Reitveld refinement. As presented in Figure 4 , the best fit of the XRD pattern is from the combination of phases LiO2 (P4/mbm), LiO4 (Ibam), and Li2O3 (Im‐3m) along with high pressure ε‐O8 phase (C2/m)22 and pristine Li2O2 phase (P63/mmc). From the fitting volumetric percentage, the amount of LiO2 is quite small (3.27%), but the amount of Li2O2 has increased dramatically. The following chemical reactions can be considered
High pressure XRD pattern after laser heating at 48 GPa and the corresponding Reitveld refinement with four high pressure oxides and ε‐O8 phases. The black dotted and continuous red curves are experimental and refined diffraction patterns. ...
In the above redox reactions, the LiO2 is mainly an intermediate product and largely converted to Li2O3 and LiO4 phases. At this high pressure, only the P4/mbm phase of LiO2 is observed, and the Li2O2 has the same structure as that at ambient pressure, consistent with the conclusion from run 1. Because of the thermal insulator layers of LiF, the diamond anvils survived, and no carbon was involved in the redox reaction at 48 GPa. In the above redox reactions, the LiO2 takes a new form as P4/mbm structure, whereas the LiO4 stays at Ibam phase. Additionally, the stable Li2O3 phase can be successfully detected from the powder diffraction. The strong peak at 2θ = 7° was attributed to the ε‐O8 phase.22 Based on DFT calculations, although the LiO2 is a thermally stable phase under high temperature and pressure, it is largely combined with Li2O2 and O2 to form Li2O3 and LiO4, respectively, and LiO2 itself becomes less stable at high temperature and may decompose into Li2O2 and O2, or Li2O2 and LiO4. This decomposition might lead to only a small percentage of LiO2 at 48 GPa (only 3.27%).
Comparing the DFT calculation and experimental results, we notice the discrepancy of Li2O3 phase in different pressures. Although the Li2O3 is predicted as a stable phase starting at 15 GPa by DFT calculation, we did not observe this structure with XRD; but at 48 GPa, more than 1/3 of the diffraction intensity was attributed to Li2O3. The DFT calculations did not indicate this phase at this pressure, as shown by the convex hulls in Figure Figure2.2. This discrepancy between DFT calculation and experimental observation could be due to the high kinetic energy of the Li2O3 phase. At 14.4 GPa, the pressure and temperature are not enough to overcome the kinetic barrier to form Li2O3 phase, although thermodynamically it is stable; at 48 GPa, however, the pressure and temperature bring Li2O3 to a metastable phase, as we observed experimentally despite the DFT calculation not favoring formation of this phase at this pressure. Authors noticed a similar DFT calculation work was posted on arXiv, where some lithium‐rich lithium oxides are predicted as well.23
In conclusion, under high pressure and temperature, several stable phases of oxygen‐rich lithium oxides can be synthesized (see Figure 5 ). Combining the DFT predictions and in situ structural measurements at high pressure, we have successfully confirmed three new stable oxygen‐rich lithium oxide phases: LiO2 (P4/mbm), Li2O3 (Im‐3m), and LiO4 (Ibam). Also, the Li2O2 phase (P63/mmc) is robustly stable up to 57 GPa at room temperature. The high pressure LiO2 and LiO4 phases can be considered as lithium atoms inserted between the layers of ε‐O8 phase, while the Li2O3 structure inherits the local atomic arrangements from the ambient Li2O2 and LiO2 (Pnnm) structures. At increasing temperature, the high‐pressure LiO2 (P4/mbm) phase losses its stability and converts to LiO4 and Li2O3 or decomposes to Li2O2 and O2. This variety of lithium oxides provides a rich field for discovering candidate electrode materials for lithium–oxygen batteries. For instance, the LiO4 phase could offer an opportunity of using the material as electrode for a close and novel lithium oxygen cell since LiO4 can provide the O2 needed in this case.
Crystal structures of five lithium oxide and ε‐O8 phases. The atomic structure arrangements in unit cell: a) ambient pressure Li2O2 (P63/mmc), b) ambient pressure LiO2 (Pnnm), c) high pressure LiO2 (P4/mbm), d) high pressure LiO4 (Ibam), ...
High Pressure XRD Measurement: Synchrotron XRD measurements in the angle‐dispersive diffraction mode were conducted in a diamond anvil cell at beamlines 16BM‐D and 16ID‐B by the High Pressure Collaborative Access Team (HPCAT) at the Advanced Photon Source, Argonne National Laboratory. The monochromatic beam was focused to around 5–10 µm full width at half maximum, and the powder diffraction patterns were recorded by a Mar345 image plate at the 16BM‐D station and a Pilatus 1M detector at the 16ID‐B station. The 2D patterns were integrated to a 1D profile with Fit2d software, and the Rietveld structural refinements were conducted with the GSAS package.24
For the first run, the X‐ray wavelength was 0.4123 Å, and the pressure was calibrated by the ruby luminescence method. In the second run, a mixture of Li2O2 powder and liquid oxygen was compressed to 15 GPa, followed by high power laser heating to 2200 K. This heat treatment vaporized the carbon from the anvil surface, which did not have a thermal insulating layer, thus adding a small amount of carbon to the chemical reaction. The surface damage of the anvil after laser heating showed clear evidence of missing carbon from the anvil. The X‐ray wavelength used was 0.39 995 Å. On the third run, with the help of thermal insulator layers of LiF, no diamond anvil damage was observed after laser heating to above 2000 K. The X‐ray wavelength used was 0.40 663 Å. In both runs 2 and 3, no ruby was loaded in the diamond anvil cells to avoid the possible chemical reaction during laser heating. The pressures were calibrated with the diamond Raman signal. For the final comparison run on the mixture of Li2O2 and oxygen at room temperature up to 53 GPa, the X‐ray wavelength used was the same as third run. Since no heat treatment was involved, a small Ruby ball was loaded in the sample chamber as pressure calibrant.
Ab Initio Crystal Structure Searching: The first principle calculations were performed in the framework of density functional theory25, 26 through the package VASP.27 The generalized gradient approximation of Perdew, Burke, and Ernzerhof was implemented to describe the exchange correlation functions.28, 29 Pseudopotentials were used with 3 valence electrons for Li (1s22s1) and 6 for O atoms (2s22p4). For crystal structure searching, we used USPEX with a plane‐wave basis set cutoff energy of 800 eV.
Phonon Dispersion Curves from First Principles: Phonon calculations were conducted based on density functional perturbation theory30 implemented in VASP software in connection with phonopy software.31 It was found that phonon dispersions are stable for LiO2, Li2O3, and LiO4 at 14.4 and 48 GPa, as shown in Figure S4 (Supporting Information).
The authors thank Chuanlong Lin for beamline technical support. This project was supported by the NSAF funding (U1530402). W.Y. and H.‐K.M. acknowledge the financial support from the DOE‐BES X‐ray Scattering Core Program under Grant No. DE‐FG02‐99ER45775. The XRD measurements were performed at HPCAT, the Advanced Photon Source (APS), Argonne National Laboratory in USA. HPCAT operations are supported by the DOE‐NNSA under Award No. DE‐NA0001974 and the DOE‐BES under Award No. DE‐FG02‐99ER45775, with partial instrumentation funding by the NSF. The APS is supported by the DOE‐BES, under Contract No. DE‐AC02‐06CH11357.
Yang W., Kim D. Y., Yang L., Li N., Tang L., Amine K., Mao H.‐K., Adv. Sci. 2017, 4, 1600453 https://doi.org/10.1002/advs.337
Wenge Yang, Email: nc.ca.ratsph@gwgnay.
Duck Young Kim, Email: email@example.com.