# X-Ray-Induced Changes to Passivation Layers of Lithium-Ion Battery Electrodes

Authors: Benjamin T. Young; David R. Heskett; Joseph C. Woicik; Brett L. Lucht
Journal: Journal of Spectroscopy
 (2018)

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## Abstract

The surface sensitivity available to photoelectron spectroscopies (PESs) makes them popular techniques for characterization of chemical environments at shallower depths than other, more bulk-sensitive techniques and because they are generally thought to be nondestructive. Variable energy, synchrotron radiation (SR), permits access to information not available to common lab-based radiation sources, making high-energy PES studies extremely useful for understanding thin films and interfaces. High-SR photon flux has been useful for developing models of soft X-ray-induced effects, but hard X-ray SR-induced effects are less well studied and will be increasingly important as popularity and availability of SR for thin film analysis continues to grow. We report here on observed modification of the solid electrolyte interphase of a lithium-ion battery electrode during prolonged exposure to 4 keV SR. The effects can be summarized by desorption of oxygen-containing species from the sample surface and by reactions within the film. Also presented is an estimate of the layer thickness’ time evolution during the prolonged SR exposure.


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## Body

## 1. Introduction

Modifications of surfaces under spectroscopic investigations had been of interest, albeit mostly for technical manufacturing reasons [1], since before the observations of Redhead [2] and of Menzel and Gomer [3, 4] in the 1960s. These studies reported desorption of ions of oxygen, hydrogen, carbon monoxide, and barium from adsorbed layers on metals under bombardment by low-energy electrons. The Menzel–Gomer–Redhead (MGR) model that developed in 1964 describes the mechanism responsible for their observations as a direct valence excitation that produces dissociation or desorption of the adsorbate, and the subsequent success of the MGR model helped electron-stimulated desorption (ESD) to become promising techniques for material investigations of many systems.In the late 1970s and early 1980s, the Knotek–Feibelman (KF) model was developed to reinterpret ESD data that were not entirely consistent with the predictions of the MGR model [5–9]. The KF model identifies the primary process as core-level excitation, followed by Auger decay(s). This model is particularly suited to highly ionic systems and provides a natural extension to higher energy excitation, as well as to excitation by photons in photon-stimulated desorption (PSD), X-ray PSD (XPSD), and X-ray-induced electron-stimulated desorption (XESD) studies.The MGR and KF models as well as subsequent refinements to the theoretical understanding, including covalent systems [10], neutral fragments [11], lithography [12], defect-electron spreading [13], decomposition [14–17], and others have helped to maintain ESD/PSD popularity and utility for many years and have motivated the exploitation of the phenomena for various purposes. Urisu and coworkers demonstrated oxygen desorption from molybdenum oxide via synchrotron radiation (SR) as a viable means of surface cleaning [18], and a considerable focus on preferential photochemical reactions highlights the possibilities for deposition and doping in materials engineering applications [19–22].Soft X-rays are common photon sources for these experiments as much of the theoretical interest involves excitation of core-levels with electron-binding energies in the sub-keV range. Chou and Wen note, however, that while many soft X-ray sources and their characteristic photon flux densities are generally assumed to cause negligible changes to the adsorbate in PSD studies, particular systems can exhibit variation in chemical-bonding structure, especially when high-intensity SR is used [23]. When hard X-ray sources are used, in addition to the MGR and KF model mechanisms, escaping photoelectrons contribute to a high-energy secondary electron background. As the energy of the exciting photons increases, in contrast to the KF model (where the energy of the generating Auger event is necessarily fixed) and the MGR model (where the cross section for direct ionization of valence electrons decreases), higher‐energy electron‐stimulated effects will become more important. As Rosenberg and coworkers pointed out, the availability of high-energy SR motivates novel applications such as deep X-ray lithography [24]. In that study, the authors demonstrated etching and deposition by irradiating substrates immersed in reactive solvents as well as fabrication of nanocrystalline particles. Core-level excitations from high-energy photons give enough energy to escaping photoelectrons to break chemical bonds, and the ability of the photons to modify the sample can scale with the energy.Certainly, as the high energy and high flux of SR continue to find more applications in the fields of thin film systems and materials science at large, changes induced by the interaction of SR with the samples being studied will be important to consider. The deeper penetration of high-energy photons will make secondary, KF model-like, and other processes more important. Flege et al. have shown that X-ray standing waves (XSW) using electrons and fluorescence photons as secondary signals with XPSD (XSW-PSD) is a viable tool to investigate desorption with the ability to identify the underlying direct or indirect processes in a site-specific manner for several systems (see [25] and references therein) with photon energies in the HAXPES range. In the present work, we report on observations of structural and chemical changes to a complex passivation layer on a silicon nanoparticle substrate using 4 keV SR.The solid electrolyte interphase (SEI) is a passivation layer that grows on electrodes in lithium-ion batteries (LIBs) during normal charge/discharge cycling. Development of chemistries to promote a superior SEI is one part of the ongoing effort to improve secondary battery performance [26–28]. Many methods being employed to improve performance may be better understood by hard X-ray photoelectron spectroscopy (HAXPES) investigation or by the more common, lower energy version of this technique, XPS, which differs from HAXPES [29–33]. The SR-based HAXPES technique is able to provide additional information due to the higher-energy photons available from synchrotron sources [34–39]. Most lab-based XPS experiments provide photons with one or two distinct energies (1487 eV Al-Kα or 1254 eV Mg-Kα), whereas SR gives access to photons with energy up to 10 keV. The greater energy given to escaping photoelectrons in HAXPES experiments provides information from greater mean depth in the SEI than what is obtained from XPS (roughly double, in this investigation), and the tunability of SR enables characterization of the SEI at multiple depths in HAXPES experiments. Included in the supplemental information for this report is a comparison of the mean free path for core electrons in lab-based XPS instruments with HAXPES experiments.The HAXPES technique can be extremely useful to the LIB effort, but care must be taken to understand the effects of SR irradiation, especially as they concern modifications to the SEI. Edstrom et al. note that attention was paid to these concerns by monitoring the C 1s and F 1s spectra during data collection and decreasing the radiation intensity [35]. However, to our knowledge, neither the nature nor the extents of the X-ray-induced changes we report here have been systematically studied.


## 2. Materials and Methods

For the present study, we analyzed a binder-free silicon nanoparticle electrode after 20 charge/discharge cycles in a coin-cell Li-ion battery built with 1.2 M LiPF6 electrolyte salt in fluoroethylene carbonate (FEC) as solvent (half-cell). Preparation, charge/discharge cycling, and disassembly of the battery from which the sample analyzed in this study was harvested has been previously published in our study regarding the formation of the SEI for this system [37]. The harvested electrode was dried overnight in the vacuum antechamber of the Ar-filled glovebox in which the battery was disassembled, installed in a tightly sealed vessel under Ar at atmospheric pressure, and transported to the X-24A endstation of the NIST beamline at the National Synchrotron Light Source (NSLS-I), Brookhaven National Laboratory (Upton, NY), for analysis. At the beamline, the vessel was opened in a glovebag attached to the fast-turnaround load lock port of the endstation as a positive pressure of N2 was flown outward through the bag. We recorded spectra for the C 1s, P 1s, Si 1s, and O 1s cores in that order and spending equal time scanning each region, so one complete collection period took 25 minutes. This time is roughly what it takes to collect all cores for a given sample at a given photon energy in one of our HAXPES studies. To elucidate the changes SR induced, we repeated 25-minute collection periods back to back for a total SR exposure of more than three hours.Estimates for the SEI layer’s relative thickness during SR irradiation are performed using the Si 1s core signal, similar to our previous work [39], but since there is no unchanging species that is localized to the substrate and obviously apparent in this system, as the metal oxide signal was in that study, we have reported thickness estimates relative to the initial measurements of two peaks (LixSiOy and LixSi) in the Si 1s spectrum representing the interface between the SEI and the substrate silicon nanoparticles.The thickness approximation is described by the following equation:(1)CiCf=∫d∞e−x/λsinθdx∫0∞e−x/λsinθdx≈e−d/λ,where the ratio of the concentration Ci in a given sample to the concentration Cf in the fresh sample equates to an exponential which is readily solved for d, the thickness of the sample. The inelastic mean free path of polyethylene was used for λ [40]. The angle between the analyzer line of sight and the surface normal to the sample defines θ, which was fixed at 3°. Concentrations were calculated according to the following equation:(2)Ci=Ai/TKEiσhνiλKEi∑jAj/TKEjσhνjλKEj,where A corresponds to the spectrum area after Shirley background subtraction and normalization to the background level, T is the relative transmission function of the X-24A analyzer [41], σ is the Scofield photoionization cross section [42], λ is defined as above, and the summation index j runs over all distinct elements analyzed. The Si 1s concentration was separated for this analysis and restricted to include only the areas of the LixSiOy and LixSi peak contributions, as obtained through fits to the experimental data using Voigt shapes.


## 3. Results and Discussion

While there were no observable changes to the spectra between individual spot tests at different locations on the sample and the first displayed period of data collection, we observe changes to all collected spectra between the first and second periods of data collection. Selected spectra are presented in Figure1 as plots of intensity versus electron-binding energy in eV. The spectra are arrayed in four panes, each representing one of the four cores, and each pane displays the progression of the spectrum relative to the time of beam exposure. Several traces are displayed for time intervals between one and seven multiples of 25 minutes, representing the beginning of each four-core period of data collection. We saw no obvious further changes to the spectra for beam exposure times longer than 175 minutes.Figure 1
Individual 1s electron spectra for (CW from top left) C, P, Si, and O for BF-Si nanoparticle electrode after 20 charge/discharge cycles in FEC solvent, displayed in increments of 25 min. of exposure to 4 keV photon flux (∼200 J of energy). Noise in the P 1s spectrum is due to the small concentration of phosphorus in the SEI and the desire to minimize data collection time.The most striking features in Figure1 are observed in the C 1s (upper left) and O 1s (lower left) spectra. In the carbon spectrum, there is a very clear reduction in the signals we have assigned to species with C-O (286.5 eV), CO3 (289.7 eV), and C-F (291 eV) bonds. In the oxygen spectra, the major feature is the reduced intensity of the shoulder on the high‐binding energy‐side of the broad peak. We assign this shoulder to the C-O bond (binding energy 534.5 eV), consistent with the concomitant change in the carbon spectra. These changes can be explained by desorption of oxygen-containing species from the surface layer. That the Li2CO3 intensity is not obviously changed in the carbon and oxygen spectra supports the suggestion from our previous work that this species is more prevalent deeper in the SEI [37] and/or is less sensitive to beam exposure. The reduction of the C-F signal intensity at 291 eV is likely due to carbonization of sequestered FEC (or its decomposition products [43]) similar to what has been reported for observations on the polymer polyvinylidene fluoride, a very popular binder material for Li-ion electrode fabrication [33, 36], upon exposure to soft X-rays [15, 16]. In Figure 2, the integrated intensity of each spectrum is plotted against exposure time, and the curves are normalized to the initial observed intensity for each element. The carbon and oxygen traces both decrease in a roughly linear, nearly identical fashion in time consistent with photon-stimulated desorption proportional to the energy delivered to the sample by a photon beam of constant energy and nearly constant flux.Figure 2
Total signal intensity vs. beam exposure time for the 1s electrons of Si, P, O, and C normalized to the initial intensity from BF-Si nanoparticle battery electrode after 20 charge/discharge cycles in FEC solvent. Uncertainty in these measurements, propagated from the fit areas, is less than 10% for all measurements. Energy incident on the sample from the 4 keV photon beam is estimated to be 1.5 J after 3 hours.We estimate the energy incident on the sample during each 25-minute data collection period to be roughly 200 mJ (at a flux of approximately 2.1 × 1012 photon s−1) as an upper limit based on published photon flux ranges delivered to the beamline from the storage ring, the beamline optics, as well as the geometry of the sample and its orientation relative to the photon beam [44–46].By contrast, the phosphorus trace in Figure2 indicates very little change in total intensity versus time. The phosphorus trend is less clear than the other three traces in Figure 2 owing to the relatively lower signal/noise for P 1s spectra of Figure 1. This is to be expected as less than 1% of the total signal observed comes from phosphorus-containing species, and the collection time was kept constant across all four cores to minimize the collection period. Inspecting the P 1s progression in the top right pane of Figure 1, however, reveals the relatively constant total (integrated) phosphorus signal is a result of intensity redistribution indicating recombination. The P 1s spectra, show a clear reduction in intensity of the higher-binding energy peak attributed to unmodified electrolyte salt LiPF6 (2151.5 eV) trapped in the SEI, and an increase in the intensity of the broad peak at lower binding energy assigned to fluorinated lithium phosphates. This result is consistent with photon-stimulated decomposition of the LiPF6 salt, as phosphates are an expected product of its decomposition [47].The total intensity for silicon species in Figure2 is nonlinear in time, increasing dramatically for the first few 25-minute measurement periods and less so for further irradiation, and finally approaching an apparent asymptote for exposure longer than about two hours, which we estimate to be equivalent to 1 J of absorbed energy from the 4 keV photon beam. This result is mirrored in the Si 1s spectra displayed in Figure 1, where all peaks appear to gain some intensity in time with nothing obviously decreasing. Desorption from the SEI indicated in the carbon and oxygen spectra may impact the layer thickness to such an extent that more of the substrate silicon is visible to the technique, which is consistent with the apparent intensity increases of all identified silicon-containing species. Estimation of the relative thickness decrease of the SEI layer is reported in Figure 3 as calculated from Voigt fits to the peaks in the Si 1s spectra we have identified as LixSi and LixSiOy. The measurements from the two peaks agree well within the uncertainty of the measurements. We estimate that the SEI thickness is decreased by about 1 nm after three hours of SR irradiation (∼1.5 J) but at that point the thickness does not appear to be markedly changing. We have recently estimated the SEI thickness developed on different systems [39] and found the total SEI thickness to be on the order of tens of nanometers.Figure 3
Thickness estimates for the SEI calculated relative to the initial measurement of the Si 1s core excited with 4 keV photons for the peak we identified as LixSi (open markers) and LixSiOy (solid markers). Uncertainty in these estimates, propagated from the fit areas, is less than 10% for all measurements. Energy incident on the sample from the 4 keV photon beam is estimated to be 1.5 J after 3 hours.


## 4. Conclusions

We have analyzed the evolution of a complex, passivating SEI layer grown on the BF-Si electrode of a LIB after 20 charge/discharge cycles to document the changes that are observed due only to SR irradiation during ex situ analysis. We have observed modification of the SEI consistent with desorption of oxygen- and carbon-containing species as well as conversion between phosphorus-containing species. We are able to estimate how much thickness of the layer is lost to desorption and find it to be slightly more than 1 nm after more than three hours of SR irradiation, which we estimate to be equivalent to 1.5 J of energy from the 4 keV photon beam. Relative to the estimated thickness of SEIs from similar systems, this loss accounts for less than 5% of the total layer thickness for exposure to SR well in excess of our usual data collection time.



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*Source: 1075902-2018-11-01.xml*