Academic literature on the topic 'Post-spinel phase transition'

AbstractThe 660-kilometre seismic discontinuity is the boundary between the Earth’s lower mantle and transition zone and is commonly interpreted as being due to the dissociation of ringwoodite to bridgmanite plus ferropericlase (post-spinel transition)1–3. A distinct feature of the 660-kilometre discontinuity is its depression to 750 kilometres beneath subduction zones4–10. However, in situ X-ray diffraction studies using multi-anvil techniques have demonstrated negative but gentle Clapeyron slopes (that is, the ratio between pressure and temperature changes) of the post-spinel transition that do not allow a significant depression11–13. On the other hand, conventional high-pressure experiments face difficulties in accurate phase identification due to inevitable pressure changes during heating and the persistent presence of metastable phases1,3. Here we determine the post-spinel and akimotoite–bridgmanite transition boundaries by multi-anvil experiments using in situ X-ray diffraction, with the boundaries strictly based on the definition of phase equilibrium. The post-spinel boundary has almost no temperature dependence, whereas the akimotoite–bridgmanite transition has a very steep negative boundary slope at temperatures lower than ambient mantle geotherms. The large depressions of the 660-kilometre discontinuity in cold subduction zones are thus interpreted as the akimotoite–bridgmanite transition. The steep negative boundary of the akimotoite–bridgmanite transition will cause slab stagnation (a stalling of the slab’s descent) due to significant upward buoyancy14,15.

Crystal structures and electrochemical reactivities of high-pressure forms of the lithium titanium spinel Li[Li_1/3Ti_5/3]O₄ (LTO) were investigated under a pressure of 12 GPa to elucidate its structural phase transition from spinel to post-spinel and to obtain a wide variety of electrode materials for lithium-ion batteries.

The dependence on lithium for rising global energy demand coupled with the scarcity of lithium necessitates the exploration of post-lithium strategies. Calcium-ion batteries are one such post-lithium strategy that can mitigate rising costs owing to calcium’s natural abundancy. A critical gap in this field is the lack of cathodes capable of intercalating calcium at high voltages and capacities while also retaining structural stability. The handful of candidates evaluated thus far have been plagued by low capacities and poor cycling performance due to intercalation–induced phase changes and instability. Transition metal oxide post–spinel–type materials have been identified as potential candidates for reversible Ca–ion storage owing to their crystal structures and high theoretical energy densities. However, experimental validation of these theoretical predictions remains largely unaddressed. In this work, post-spinel Calcium Iron Oxide (CaFe2O4) and Calcium Manganese Oxide (CaMn2O4) are explored as cathodes for calcium-ion batteries. The redox activity of each cathode is investigated using galvanostatic (GS) cycling while their structural stabilities are evaluated with X-ray diffraction (XRD) and scanning electron microscopy (SEM). The use of GS in tandem with XRD and SEM provides insights into the evolution of crystal structure with Ca–ion–transport within each cathode. Our results reveal that these post–spinel systems can cycle with a reversible capacity of 56 mAh/g, making them promising cathode candidates for Ca–ion batteries and warrant further investigation.

The Clapeyron slope is the slope of a phase boundary in P–T space and is essential for understanding mantle dynamics and evolution. The phase boundary is delineating instead of balancing a phase transition’s normal and reverse reactions. Many previous high pressure–temperature experiments determining the phase boundaries of major mantle minerals experienced severe problems due to instantaneous pressure increase by thermal pressure, pressure drop during heating, and sluggish transition kinetics. These complex pressure changes underestimate the transition pressure, while the sluggish kinetics require excess pressures to initiate or proceed with the transition, misinterpreting the phase stability and preventing tight bracketing of the phase boundary. Our recent study developed a novel approach to strictly determine phase stability based on the phase equilibrium definition. Here, we explain the details of this technique, using the post-spinel transition in Mg2SiO4 determined by our recent work as an example. An essential technique is to observe the change in X-ray diffraction intensity between ringwoodite and bridgmanite + periclase during the spontaneous pressure drop at a constant temperature and press load with the coexistence of both phases. This observation removes the complicated pressure change upon heating and kinetic problem, providing an accurate and precise phase boundary.

In recent years, extensive research has been performed on high energy cathode materials for lithium ion batteries being used in electric vehicles to reduce carbon emissions. Compared to the commercial layered cathode materials, the absence of cobalt in the spinel LiMn1.5Ni0.5O4 (LMNO) makes this material more environmentally friendly and cheaper.1 Spinel LMNO cathodes also reveal attractive gravimetric and volumetric energy densities of 635Whkg−1 and 2820WhL−1, respectively.2 According to the distribution of transition metals (TM) within the cubic crystal structure, spinel LMNO can be categorized into either ordered or disordered. Normally, disordered LMNO materials are produced at temperatures higher than the theoretical oxygen release temperature of spinel LMNO (715 °C).3 The formation of O vacancies is accompanied by some Mn4+ atoms being reduced to Mn3+ to maintain the electroneutrality of spinel LMNO. Ordered LMNO can be obtained through calcination at temperatures lower than 715 °C or post-annealing disordered LMNO materials at 700 °C.4 The reversible extraction and insertion of O atoms accompanied with different distribution of TM during spinel LMNO preparation drive up a hypothesis that the oxygen activity during cycling of spinel LMNO may be affected by the distribution of TM atoms, especially since the operating voltage of spinel LMNO (> 4.7 V) is high enough to trigger oxygen redox in other lithium transition metal oxides.5 To explore the feasibility of oxygen activity during cycling of spinel LMNO, the normal, core-shell and sandwich designed synthesis are performed using special Mn0.75Ni0.25(OH)2 precursors to arrange different distributions of TM atoms in the obtained N-, CS- and SW-LMNO. As shown in Figure 1(a) – (c), the three materials show similar XRD patterns in the pristine state, yet different reflection peaks are observed in the three materials after charging to 4.9 V. The unclear phase transition of SW-LMNO indicates it show stable structure. The three materials also show different CV curves, see Figure 1(d). This indicates the extraction and insertion of Li atoms lead to different redox reactions in the three materials. Besides, differential electrochemical mass spectrometry (DEMS), in-situ transmission electron microscope (TEM) as well as hard and soft X-ray absorption spectroscopy (XAS) measurements are utilized to further investigate the oxygen activity during cycling of spinel LMNO. Reference 1. Li, M. & Lu, J. Cobalt in lithium-ion batteries. Science 367, 979-980 (2020). 2. Hagh, N. M. & Amatucci, G. G. A new solid-state process for synthesis of LiMn1. 5Ni0. 5O4−δ spinel. Journal of Power Sources 195, 5005-5012 (2010). 3. Manthiram, A., Chemelewski, K. & Lee, E.-S. A perspective on the high-voltage LiMn1.5Ni0.5O4 spinel cathode for lithium-ion batteries. Energy & Environmental Science 7, 1339-1350 (2014). 4. Chemelewski, K. R., Shin, D. W., Li, W. & Manthiram, A. Octahedral and truncated high-voltage spinel cathodes: the role of morphology and surface planes in electrochemical properties. Journal of Materials Chemistry A 1, 3347-3354 (2013). 5. Seo, D.-H. et al. The structural and chemical origin of the oxygen redox activity in layered and cation-disordered Li-excess cathode materials. Nature chemistry 8, 692-697 (2016). Figure 1. Operando X-ray diffraction patterns of N- (a), CS- (b) and SW- (c) LiMn1.5Ni0.5O4 in the pristine states and at the charge states of 4.9 V and the corresponding cyclic voltammetry curves of the three materials (d) Figure 1

The metastable olivine (Ol) wedge hypothesis assumes that Ol may exist as a metastable phase at the P conditions of the mantle transition zone (MTZ) and even deeper regions due to inhibition of the phase transitions from Ol to wadsleyite and ringwoodite caused by low T in the cold subducting slabs. It is commonly invoked to account for the stagnation of the descending slabs, deep focus earthquakes and other geophysical observations. In the last few years, several new structures with the forsterite (Fo) composition, namely Fo-II, Fo-III and Fo-IV, were either experimentally observed or theoretically predicted at very low T conditions. They may have important impacts on the metastable Ol wedge hypothesis. By performing first-principles calculations, we have systematically examined their crystallographic characteristics, elastic properties and dynamic stabilities from 0 to 100 GPa, and identified the Fo-III phase as the most likely metastable phase to occur in the cold slabs subducted to the depths equivalent to the lower part of the MTZ (below the ~600 km depth) and even the lower mantle. As disclosed by our theoretical simulations, the Fo-III phase is a post-spinel phase (space group Cmc21), has all cations in sixfold coordination at P < ~60 GPa, and shows dynamic stability for the entire P range from 0 to 100 GPa. Further, our static enthalpy calculations have suggested that the Fo-III phase may directly form from the Fo material at ~22 GPa (0 K), and our high-T phase relation calculations have located the Fo/Fo-III phase boundary at ~23.75 GPa (room T) with an averaged Clapeyron slope of ~−1.1 MPa/K for the T interval from 300 to 1800 K. All these calculated phase transition pressures are likely overestimated by ~3 GPa because of the GGA method used in this study. The discrepancy between our predicted phase transition P and the experimental observation (~58 GPa at 300 K) can be explained by slow reaction rate and short experimental durations. Taking into account the P-T conditions in the cold downgoing slabs, we therefore propose that the Fo-III phase, rather than the Ol, highly possibly occurs as the metastable phase in the cold slabs subducted to the P conditions of the lower part of the MTZ (below the ~600 km depth) and even the lower mantle. In addition, our calculation has showed that the Fo-III phase has higher bulk seismic velocity, and thus may make important contributions to the high seismic speeds observed in the cold slabs stagnated near the upper mantle-lower mantle boundary. Future seismic studies may discriminate the effects of the Fo-III phase and the low T. Surprisingly, the Fo-III phase will speed up, rather than slow down, the subducting process of the cold slabs, if it metastably forms from the Ol. In general, the Fo-III phase has a higher density than the warm MTZ, but has a lower density than the lower mantle, as suggested by our calculations.

Lithium-rich layered oxides are recognized as promising materials for Li-ion batteries, owing to higher capacity than the currently available commercialized cathode, for their lower cost. However, their voltage decay and cycling instability during the charge/discharge process are problems that need to be solved before their practical application can be envisioned. These problems are mainly associated with a phase transition of the surface layer from the layered structure to the spinel structure. In this paper, we report the AlF3-coating of the Li-rich Co-free layered Li1.2Ni0.2Mn0.6O2 (LLNMO) oxide as an effective strategy to solve these problems. The samples were synthesized via the hydrothermal route that insures a very good crystallization in the layered structure, probed by XRD, energy-dispersive X-ray (EDX) spectroscopy, and Raman spectroscopy. The hydrothermally synthesized samples before and after AlF3 coating are well crystallized in the layered structure with particle sizes of about 180 nm (crystallites of ~65 nm), with high porosity (pore size 5 nm) determined by Brunauer–Emmett–Teller (BET) specific surface area method. Subsequent improvements in discharge capacity are obtained with a ~5-nm thick coating layer. AlF3-coated Li1.2Ni0.2Mn0.6O2 delivers a capacity of 248 mAh g−1 stable over the 100 cycles, and it exhibits a voltage fading rate of 1.40 mV per cycle. According to the analysis from galvanostatic charge-discharge and electrochemical impedance spectroscopy, the electrochemical performance enhancement is discussed and compared with literature data. Post-mortem analysis confirms that the AlF3 coating is a very efficient surface modification to improve the stability of the layered phase of the Li-rich material, at the origin of the significant improvement of the electrochemical properties.

The demand for high-capacity batteries is increasing rapidly with the upcoming energetic needs of an ever increasing population, especially in the transportation sector. Lithium-ion battery (LIB) has emerged as an attractive technology, however the main restriction is his low energy density1. To make a post-transition possible the sodium-ion battery (SIB) are among the most promising alternatives due sodium is abundant, there are enormous availability and It's low cost2. Besides, the electrochemical principles governing LIB and SIB batteries are quite similar3. Nevertheless, for both emerging alternatives it is necessary to find more suitable electrode materials. Therefore, nowadays, different electrode materials have been explored to increase the capacity of those batteries. Specially, the layered-spinel structure has been used to improve the initial specific capacity and stability electrode materials. The Na-layered structure cathode facilitates Li+-ion diffusion in the structure4. Besides the incorporation of Ti4+ in the LiMn2O4 spinel phase is performed with the purpose of improving its stability by averting the Jahn-Teller effect of the Mn3+ and decreasing Mn2+ dissolution towards the electrolyte during cycling since Ti-O provides a higher binding energy (662 kJ/mol) than for Mn-O (402 kJ/mol)1. The aim of this investigation is to estimate the optimal stoichiometry in the (1-x)Li1-yNayM1-zTizO2x LiM2-zTizO4 layered-spinel by varying the concentration of Na+ and to assess the effects of the cations addition in the cycling stability of the active material. A facile sol-gel method is presented to develop new composite materials for LIB and SIB. Cathode materials were characterized by XRD, Raman, SEM, VC, EIS and charge/discharge cycling tests. Analysis of XRD patterns confirmed the existence of a spinel-layered composite where the peaks can be indexed to the cubic spinel structure ( space group) and layered structure (C 12 - m1; R-3m and P 63-mmc space group)°5. For LIB cycling was performed typically between 4.8 and 2.0V vs. Li|Li+ at a constant current of 29.0 mAg-1, equivalent to 0.1 C-rate. The stoichiometry 0,5Li0.9Na0.1Mn0.4Ni0.5Ti0.1O2-0,5LiMn1.4Ni0.5Ti0.1O4 showed an initial specific capacity, ca. 141 mAhg-1 but later it presented increasing of the specific capacity, ca. 180 mAh g-1 at 15st cycling exhibiting 98% of its charge capacity after 30st cycles. Moreover, for SIB cycling was performed typically between 4.5 and 2.0V vs. Na|Na+ at a constant current of 10.0 mAg-1, equivalent to 0.1 C-rate. In this case, the stoichiometry 0,5Li0.5Na0.5Mn0.4Ni0.5Ti0.1O2-0,5LiMn1.4Ni0.5Ti0.1O4 showed an initial specific capacity, ca. 94 mAh g- 1. Thus, by possessing interesting properties electrochemical we believe that these materials could be a potential electrode for the development of high-power rechargeable Li-ion batteries and Na-ion batteries. References N. Mosquera, F. Bedoya-Lora, V. Vásquez, F. Vásquez, and J. Calderón, Journal of Applied Electrochemistry (2021) https://doi.org/10.1007/s10800-021-01582-w. R. Klee, P. Lavela, and J. L. Tirado, Electrochimica Acta, 375 (2021). S. Rubio et al., Journal of Solid State Electrochemistry, 24, 2565–2573 (2020). L. Zheng and M. N. Obrovac, Electrochimica Acta, 233, 284–291 (2017) https://www.sciencedirect.com/science/article/pii/S0013468617304978. S. U. Vu. N and H. V, Journal of Power Sources, 355, 134–139 (2017) http://dx.doi.org/10.1016/j.jpowsour.2017.04.055. Figure 1

2010/2011
In questo lavoro è stata messa a punto una metodologia basata sull’analisi topologica della densità elettronica secondo la teoria di Bader che ha permesso di indagare la stabilità di fasi mineralogiche in condizioni di alta pressione. In una prima fase è stata caratterizzata la decomposizione della ringwoodite (olivina-γ) in Mg-perovskite e periclasio ( post spinel phase transition) che si ritiene essere responsabile della discontinuità sismica che si osserva a 660 Km di profondità, tra la zona di transizione del mantello ed il mantello inferiore. Lo scopo del lavoro è stato quello di ottenere informazioni sulla disposizione degli elettroni nella struttura cristallina e sulla evoluzione al variare delle condizioni di pressione. L’analisi effettuata ha mostrato l’instaurarsi di una forte instabiltà strutturale (caratterizzata da una “conflict catastrophe”) nella ringwoodite a circa 30 GPa. Tale risultato conferma il coinvolgimento della transizione di fase “post-spinel”nella discontinuità sismica a 660 Km. In una seconda fase la procedura è stata applicata alla fase Mg-perovskite allo scopo di testarne la validità. Lo studio dell’evoluzione della topologia della densità elettronica nel range di pressione da 0 a 200 GPa ha permesso di individuare una regione di stabilità della fase perovskitica (da circa 22 a circa 124 GPa) delimitata tra due “fold catastrophes”. Le due “fold catastrophes” si hanno entrambe in prossimità di discontinuità sismiche: la prima, attribuita alla transizione di fase da ringwoodite a Mg-perovskite + periclasio corrisponde alla discontinuità sismica a 660 Km e la seconda, attribuita alla transizione da Mg-perovskite a post-perovskite a circa 130 GPa, osservata a circa 2600 Km di profondità, tra il mantello profondo e il D′′-layer, poco prima della discontinuità di Gutemberg a 2900 Km.
XXIV Ciclo
1975