{'fraction_non_alphanumeric': 0.03215007055308082, 'fraction_numerical': 0.01853747613645796, 'mean_word_length': 4.482178067647505, 'pattern_counts': {'":': 0, '<': 0, '<?xml version=': 0, '>': 0, 'https://': 0, 'lorem ipsum': 0, 'www.': 0, 'xml': 0}, 'pii_count': 0, 'substrings_counts': 0, 'word_list_counts': {'cursed_substrings.json': 1, 'profanity_word_list.json': 0, 'sexual_word_list.json': 0, 'zh_pornsignals.json': 0}}
Quantifying lithium concentration gradients in the graphite electrode of Li-ion cells using operando energy dispersive X-ray diffraction

Safe, fast, and energy efficient cycling of lithium ion batteries is desired in many practical applications. However, modeling studies predict steep Li ion gradients in the electrodes during cycling at the higher currents. Such gradients introduce heterogeneities in the electrodes, which make it difficult to predict cell lifetimes as different portions of the cell age at different rates. There is a dearth of experimental methods to probe these concentration gradients across the depth of the electrode. Here we use spatially resolved energy dispersive X-ray diffraction to obtain a ‘‘movie’’ of lithiation and delithiation in different sections of the cell and quantify lithium gradients that develop in a porous graphite electrode during cycling at a 1C rate. Inhomogeneity in the total Li content, and in the individual ordered LixC6 phases formed during lithium insertion into (and extraction from) the graphite, has been observed in an operando fashion. The complex dynamics of lithium-staging in graphite with the distinct front propagation of phase changes have been characterized and new features of these dynamics are highlighted here. As large Li ion gradients contribute to cell polarization, our results suggest that Li plating conditions can be met near the graphite electrode surface, even when the cell is charged at a moderate (1C) rate.


Introduction
Faster charging of Li-ion batteries (LIBs) would enable wider adoption of electric vehicles, as it would shorten the time needed to refill these vehicles bringing it closer to consumer's expectations informed by the use of gasoline-fueled cars. The current LIBs predominantly use porous graphite (Gr) anodes (negative electrodes) and layered metal oxide cathodes (positive electrodes). At cycling rates below 1C (full discharge in 1 hour), these LIBs can go through hundreds of cycles of operation with minimal performance degradation. However, at higher cycling rates, the capacity, cycle life, and thermal stability of these LIBs is known to degrade. [1][2][3][4][5][6][7][8][9] Theoretical studies of lithium intercalation using Newman-type models 10 attribute these effects to lithium plating, kinetic losses, and Li + concentration gradients (causing polarization of the cell) occurring both in the electrolyte filling the matrix pores and in the graphite electrode itself. 9,11,12 Our focus will be the latter gradients that are a complex function of Li + diffusion coefficients, intercalation rates, ion transference numbers, and the electrode thickness (t), porosity (e), and tortuosity (t). [9][10][11] For example, low porosity and high tortuosity in the electrode decrease the effective diffusion coefficient D eff = (e/t)D bulk of the Li + ions in the matrix relative to the solvent bulk. 13,14 At high charge rates, this lower mobility leads to greater differentials in lithium concentration in the direction of the flowing Li + ion current (that we take as the z-direction of the laboratory frame with z = 0 corresponding to the electrode surface near the separator between the electrodes). 10,12,15,16 Such Li + ion gradients are problematic on at least three counts. First, they impose gradients in the lithium intercalation rates and the corresponding electrode overpotentials. 1,17,18 The latter causes polarization of the cell, so the cut-off voltage can be reached prematurely before Li is fully extracted from the cathode, resulting in a lower capacity. Second, this heterogeneous lithiation can lower the (negative) electrode potential creating conditions facilitating lithium plating, especially in regions adjacent to the separator. 9,18 Third, these Li + gradients facilitate structural stresses within the graphite particles (causing their fracture) 17,[19][20][21] and in the electrode matrix at large (causing the coating to peel off the current collector). 18,20 The higher the current flowing through the cell, the steeper the Li + gradients, and greater their effect on cell performance and life.
Graphite electrodes have particularly high tortuosities due to the high aspect ratio of the pancake-shaped flakes. 13 The effects of the packing of such particles on a cell's electrochemical performance have been demonstrated by Billaud et al. 22 Out-of-plane alignment of graphite flakes in a strong magnetic field resulted in tripling of the specific discharge capacity at 1C rate, as the axial tortuosity of the electrode matrix decreased from B14 to B3.8 after this alignment. 22 This problem is compounded by another concern inherent to the lithiated graphite as a charge storage medium: the potential for Li insertion into the graphite (85 to 220 mV vs. Li/Li + ) is perilously close to the Li plating potential, [23][24][25][26] so even a relatively small electrode overpotential can result in Li deposition on the graphite particles competing with Li intercalation into the particles.
While there have been many modeling studies of concentration gradients developing in LIBs during high-current cycling, 10 the experiments directly observing and quantifying these gradients are still lacking. With this study, we seek to close this gap in knowledge. To this end, we use energy dispersive X-ray diffraction (EDXRD) to spatially resolve Li concentration profiles during cycling of a Li-ion cell at 1C rate. With this technique, narrowly focused polychromatic (''white light'') beams of synchrotron photons are used to obtain diffraction patterns at a fixed angle y, so the Bragg condition, 2d sin y = n Â l, is satisfied for some wavelengths l in the light continuum. This method is complementary to the commonly used angle-dispersive XRD method, which uses monochromatic X-ray beams and scans the angle y to satisfy the Bragg condition. As lithium intercalates into the graphite crystal, it fills layers between the graphene sheets (''staging of the graphite'') yielding distinctive, ordered Li x C 6 phases (0 r x r 1) that can be easily recognized even from a single Bragg peak. The intensities of these peaks can be used to quantify the concentration of each Li x C 6 phase, and through such quantification we determine the exact phase composition of each probed layer in the solid matrix. As only ordered Li x C 6 phases contribute to the diffraction signal, this method is blind to Li + ions in the electrolyte and/or potential disordered solid compounds in the matrix. Using the EDXRD technique, the succession of Li x C 6 phases formed during the electrochemical lithiation and delithiation of graphite has been studied with a spatial resolution of 20 mm and a time resolution of one minute. Below we describe how this technique helps to quantify and visualize lithium gradients in the electrode and discuss the insights obtained from these data. Figures and tables with index S (e.g. Fig. S1) are contained in the ESI. †

Materials
A standard 2032-type coin cell, containing a Gr based anode and a Li 1.03 (Ni 0.5 Co 0.2 Mn 0.3 )O 2 (NCM523) based cathode, was used in our experiments. The detailed composition, sources, and properties of the cell materials are given in Table S1 (ESI †). Briefly, the anode contained 92 wt% graphite, 2 wt% conductive carbon particles, and 6 wt% polymer binder, while the NCM523 cathode contained 90 wt% oxide, 5 wt% conductive carbon particles, and 5 wt% polymer binder. The slurries were prepared by mixing the particles in a planetary centrifugal mixer using N-methyl-2-pyrrolidone as a solvent. Electrode laminates were fabricated by casting these slurries onto a 10 mm battery grade copper foil for the Gr electrode and 20 mm battery grade aluminum foil for the NCM523 counter electrode, using a battery coater at the Cell Analysis, Modeling and Prototyping (CAMP) facility at Argonne National Laboratory (ANL). After drying of the solvent, the Gr electrode was calendered to obtain uniform thickness. The NCM523 cathode was not calendered, in order to retain maximum porosity in the matrix and ensure minimal interference during the high rate cycling. Before cell assembly, the electrodes were dried at 120 1C for 12 h, and the separator was dried at 70 1C for 24 h, both in a vacuum oven. The assembled cell contained 40 mL of 1.2 M LiPF 6 in ethyl carbonate/ethyl methyl carbonate mixture (3 : 7 w/w). This electrolyte filled a microporous Celgard 2325 separator sandwiched between the two electrodes (1.58 cm 2 areas). The Gr electrode had an areal capacity of B5 mA h cm À2 ; a positive-tonegative electrode capacity ratio of 1.13 was chosen to enable deep lithiation and delithiation of the graphite electrode.

Cycling conditions
The cycling tests were conducted at 30 1C. The C-rates, state-oflithiation, and cell capacities were calculated with respect to the theoretical capacity of the Gr, which is 372 mA h g À1 . The applied current of 5.6 mA corresponded to a B1C rate for the full cell. Prior to the XRD experiment, the cell was cycled twice at a C/20 rate in the 3-4.1 V range (see Fig. S1, ESI †), in order to stabilize the solid electrolyte interphase (SEI) on the graphite electrode; this SEI protects the graphite from solvent intercalation and the electrolyte from runaway reduction reactions on the electrode. Three additional cycles were conducted during the XRD experiment: the cycling was performed in a galvanostatic regime until an upper cut voltage of 4.4 V or a lower cut voltage of 3.0 V were attained on charge (Gr lithiation) and discharge (Gr delithiation), respectively. Upon attainment of the set voltages, the cell operated in a potentiostatic regime for 30 min (referred to as ''potentiostatic hold'').

Energy dispersive X-ray diffraction (EDXRD)
The EDXRD setup at beamline 6BM-A of the Argonne's Advanced Photon Source was used to observe the diffraction patterns of the pristine graphite and ordered Li x C 6 phases in an operating Gr/NCM523 cell described above. The X-ray photons with energies between 5 and 250 keV (that corresponds to 47 to 1 Å in d-spacing) readily transmit through the stainless-steel casing of the coin cell. A Ge detector placed at a fixed angle y E 31 in the vertical plane with respect to the incident X-ray beam collected and averaged the diffraction patterns at a rate of 1 min per acquisition for a total period of 3 h per charge/ discharge cycle. The probe X-ray beam was 18.3 mm (fwhm) Â 1045 mm; this beam propagated along the plane of the Gr electrode ''slicing'' it in steps of 25 mm, to give a total of five minimally-overlapping layers numbered from L 0 to L 4 in Fig. 1 (see Section S1, ESI † for calculation of layer centroids). The X-ray power in the overlapping region was calculated to be B12% of the total beam power. The absolute position of the coin cell with respect to the X-ray beam in the transverse direction was controlled using a stepper motor, and care was exercised to perfectly align the beam with the plane of the Cu current collector. As shown in Fig. 1, layer L 0 was adjacent to the separator and layer L 4 was adjacent to the Cu current collector. In order to establish the position of the 10 mm thick Cu current collector supporting the Gr coating within the reference frame of the X-ray diffractometer stage, we took the following steps. First, the current collector was located using a coarse scanning of the incident X-ray beam along the entire thickness of the cell noting the stage position and the intensity (or absence thereof) of the Cu(002) peak at B1.808 Å d-spacing. Upon identifying a strong presence of the Cu(002) peak, a fine 5 mm step scan in a narrow 30 mm span around the Cu position was collected. By fitting a Gaussian shape to the collected intensities of the (002) peak during the scan, the estimated position of maximum intensity was taken as the midsection of the foil and used as reference in positioning the slices across the graphite electrode. To obtain the profile of the beam as it crosses the Gr matrix, a radiograph through the cell was collected (Fig. 1). The pixel intensity map represents the beam intensity distribution, which is overlaid onto the radiograph. The five layers were sampled in a round-robin fashion. To obtain the gradient plots discussed later, linear interpolation was used to bring the elucidated Li x C 6 concentrations found in the successive measurements to the same points in time.
The Li-Gr intercalation system exhibits several phases (commonly referred to as stages). Through literature review, five main stages are identified and deconvoluted from the spectra collected using their reported d-spacing ranges: dilute stage I (denoted I 0 ), stage IV/III, stage IIL, stage II, and stage I. [26][27][28][29] The following equation is used to estimate the average lithium content x of each layer (expressed in Li atoms per C 6 ): where G j = I hkl j /(m hkl j |F hkl j | 2 ), f j is the fractional Li content of the corresponding Li x C 6 phase j, I hkl j is the relative integrated flux of scattered X-ray photons from phase j, m hkl j is the multiplicity of the Bragg reflection with the Miller indices (hkl) originating from phase j in the peak region of interest, and F hkl j is the corresponding scattering factor (see Section S2, ESI † for derivation of this equation). These parameters are given in Table S2 (ESI †). Because each layer probes a different section of the cell, the corresponding X-ray fluxes have been normalized by the flux of photons scattered by the graphite in each probed layer prior to the electrochemical experiment, as explained in Section S2 (ESI †). The quantities G j = P i G i represent the  (1) gives the Li content in each phase j (per C 6 units in the graphite matrix). These quantities are independent of the material distribution, porosity, and masking of the X-ray beam by non-graphitic materials. The stoichiometry of stages I 0 and IV/III which are solid solution stages (the average Gr interlayer spacing increases with lithiation) varies with cell capacity. For these stages, a linear fit to d-spacing vs. capacity ( f j E 1.53Ád À 5.11) was used to estimate the Li content. 26

Results
The voltage-capacity curves from the Gr/NCM523 cell during cycling at a C/20 rate (cycle 2, 3-4.1 V) and a 1C rate (cycle 5, 3-4.4 V) are shown in Fig. 2. From the measured specific capacity, one can calculate the cell average lithium content % x that we express in Li atoms per C 6 unit of the graphite present in the electrode; the % x value is given at the top of Fig. 2. During 1C galvanostatic charging, the upper cut-off voltage of 4.4 V was attained at % x = 0.58, which increased to % x = 0.68 at the end of the 30 min potentiostatic hold. During the 1C discharge, the lower cut voltage of 3.0 V was attained at % x = 0.1, which decreased to % x = 0.02 at the end of the 30 min hold. Typical XRD patterns collected during the continuing cycling are shown in Fig. 3. Only X-ray data collected during the fifth cycle are given below to highlight the major features and trends observed during cell cycling; data from cycles 3 and 4 showed similar features and are included in Fig. S2 (ESI †). In the d-spacing range shown, only the major Bragg peak for each one of the Li x C 6 phases is visible. The d-spacings corresponding to these peaks are shown in Fig. 4 and their Miller indices are listed in Table S2 (ESI †). For example, stage I (LiC 6 ) is represented by (001) peak, stage II (LiC 12 ) by (002) peak, and stage IIL (LiC 18 ) by (004) peak. The peaks of stage I 0 , stage IV/III, and stage IIL overlap in d-spacing (Fig. 3). An uncertainty is introduced during deconvolution of the XRD pattern into pseudo-Voigt profiles that was used for integration; the associated errors in the quantification of lithium content can become significant especially after the formation of stage IIL (LiC 18 ).   Fig. 2). Panels (a) to (e) correspond to layers L 0 to L 4 , respectively, as labeled in Fig. 1. The diffraction intensities have been normalized by the initial intensity of the graphite in each layer and shown on the same scale. The red color corresponds to charge and the blue color corresponds to the discharge of the cell. Different Bragg peaks in this plot correspond to different ''stages'' of graphite lithiation, as explained in the text.

Paper
Energy & Environmental Science Open Access Article. Published on 09 January 2019. Downloaded on 10/5/2020 9:31:01 AM. This article is licensed under a Creative Commons Attribution 3.0 Unported Licence.

View Article Online
Another source of error arises from uncertainties in the scattering factors themselves (see Section S2, ESI †). For convenience, the concentrations of the Li x C 6 phases reported below have been adjusted by the fractional Li content f j of the phases; therefore these concentrations reflect the availability of Li in each phase averaged in a given layer.
For the slow C/20 cycle, the voltage-capacity curves shown in Fig. 2 reveal characteristic steps attributable to the graphite electrode (known as ''stages''); the stages of graphite correspond to progressive filling of spaces between the adjacent graphene sheets. As the cycling rate increases to 1C, these steps become blurred due to Li heterogeneity in the matrix, but the distinct Li x C 6 phases are seen in the X-ray diffraction patterns during layer-by-layer sectioning as shown in Fig. 3. In particular, a well-separated Bragg peak at 3.7 Å is observed, which originates from the LiC 6 phase (stage I in Fig. 4) that is formed in the final stages of lithiation. Excess Li transported to the graphite matrix beyond this final stage can become deposited as Li metal. Also clearly distinguished at the outset of charging is the rapid disappearance of dilute Li x C 6 phases that correspond to a solution of Li in graphite (stage I 0 in Fig. 4). For this stage I 0 (x o 1/8) and stage IV/III (1/4 o x o 1/3) peaks, the d-spacing changes with the extent of the lithiation x (as the unit cell dilates when the lithium content increases), whereas for stages I (x = 1), II (x = 1/2), and IIL (x = 1/3) this dependence is weak. The gaps seen in Fig. 4 correspond to lithiation regimes in which the peak positions cannot be determined due to weakness of the corresponding Bragg peaks relative to the prevalent Li x C 6 phases. For % x 4 0.3, the two prevalent phases, LiC 6 and LiC 12 , yield almost all of the diffraction signal. At peak charge (% x E 0.68, Fig. 4) the layer average lithiation x for layer L 0 as positioned in Fig. 1 is B0.87; as the LiC 6 phase permeates this layer, relatively little LiC 12 is observed.
Due to this pinning of lattice parameters and relatively strong scattering factors of LiC 6 and LiC 12 phases, their concentrations can be determined more accurately than those of the other Li x C 6 phases. In Fig. 5 we show the time progression of the LiC 6 and LiC 12 phase concentrations during cycling; the changes in the other stages/phases are included in Fig. S3 and S4 (ESI †). Near the electrode surface, the concentration profiles for lithiation and delithiation mirror each other, whereas deeper into the matrix they become asymmetric as it takes time for the formation and depletion fronts to reach the back of the electrode matrix during charging and discharging of the cell, respectively. The onset of LiC 12 formation in layer L 0 is at % x 4 0.2; for % x 4 0.4 this phase begins to convert to LiC 6 that reaches the maximum concentration of 0.72 at the peak charge. Conversely, at this peak charge, the concentration of LiC 6 in L 4 at the back of the Gr electrode is lower than 0.1, indicating a steep gradient of the LiC 6 phase in the cell.
These differences are more clearly seen in Fig. 6, in which we show the concentrations of all stages in layers L 0 and L 4 . On lithiation, the extrema stages I 0 and I decrease from a  In layer L 0 where almost complete lithiation is observed, stage I reached a maximum concentration of B0.75 in good agreement with the initial concentration of stage I 0 of 0.76. The intermediary stages IV/III, IIL, and II all show concentration peaks reflecting their formation, growth, and conversion to subsequent stages. Note that each of these three stages peak at a delayed time (that is, greater % x) in the back layer L 4 relative to their counterpart in the surface layer L 0 . As the lithiation progresses, the LiC 12 phase arises. Even in layer L 0 this LiC 12 phase is not fully replaced by LiC 6 , and residual LiC 12 remains in layer L 4 even at the peak of charge. In this deepest layer, during discharge of the cell (delithiation of graphite) the LiC 6 and LiC 12 phases also persist much longer than in the surface layer; it takes time for the lithium to flow out of the electrode before the depletion front reaches the back of the cell. Intriguingly, some of these Li x C 6 phases persist in the electrode even after the 30 min potentiostatic hold at 3 V.
Using the concentration of each phase, the layer average Li content of layers L 0 through L 4 can be determined using eqn (1) and compared with the cell average Li content % x determined electrochemically (see Fig. 7 and Table S3, ESI †). We reason that for sufficiently smooth concentration profiles the arithmetic average of these layers would be sufficiently close to the cell average (open circles in Fig. 7), i.e. the two metrics are expected to be close to each other (straight black lines in Fig. 7). This is indeed the case during charge, and this validation gives us certain confidence in our use of eqn (1). It is also seen from these plots that at the peak of charge, x for L 0 is considerably above the cell average % x, whereas x for L 4 is significantly below % x. The inhomogeneity in the quantity of individual phases in each layer across the graphite electrode (greater amount of LiC 6 at the electrode surface compared to deeper layers for example) as shown in Fig. 5 and 6 is reflected in the calculated Li content of the layers, with significant difference observed only when % x 4 0.2. A surprising feature of Fig. 7 is the asymmetry of the traces: the delithiation of the electrode does not mirror the lithiation run ''in reverse''; this asymmetry becomes even more noticeable for the deepest layers. Most strikingly, during the rapid discharge (in contrast to charge) the arithmetic mean of layer averages (open symbols in Fig. 7) strongly deviates from % x for % x 4 0.3, suggesting (among other possibilities) that the Li concentration profile may have sharp features, so our averaging of the layer Li contents becomes a poor estimate of the actual average Li concentration.
To better visualize the inhomogeneities across the electrode, in Fig. 8 we plot Li content in each layer at different states of charge as a function of the centroid depth; this information is also given in Table S3 (ESI †). The smooth lines drawn through these symbols are B-splines added as a guide to the eye. In the  initial stages of charging (Fig. 8a), the Li content is nearly uniform across the electrode. As the cell is charged further, a concentration gradient develops, with more lithium present near the surface (L 0 ) than at the back (L 4 ). This transformation nearly coincides with the moment when LiC 6 becomes the prevalent phase near the surface in this particular graphite electrode. During cell charge (Fig. 8a), the gradient d[Li]/dz remains negative across the electrode depth. During cell discharge (Fig. 8b), there is Li depletion near the surface that gradually spreads deeper into the matrix until it reaches the back of the cell. After that, the Li gradients once again become lower, and in the advanced stages of delithiation they become too small to observe. The complex shape of Li profiles during the cell discharge (Fig. 8b) compared to the profiles during the cell charge (Fig. 8a) is the primary reason for the asymmetries seen in Fig. 7, including the behavior of the arithmetic average of layer averages. In Fig. 9, we use polynomial fits to extrapolate the concentration profiles over the entire range of depth (see Section S1, ESI † for more detail). Fig. 9a and b give the color maps of Li content in LiC 6 and LiC 12 phases obtained in this manner, and Fig. 9c shows the profiles obtained at two states of charge (more of such profiles are shown in Fig. S5, ESI †). At the peak charge, a nearly exponential LiC 6 profile and an almost complete lithiation of the graphite at the electrode surface are observed. As the LiC 6 phase grows from surface towards deeper  Fig. 1 and 7 above. The smooth lines are guides to the eye. The numbers in the plot give the overall cell average lithium content of the graphite matrix calculated based on the electrochemically measured cell capacity. This observation is made more obvious in Fig. 9c and also from comparison of Fig. 9a and b: the crest of high concentrations of LiC 6 in Fig. 9a maps exactly onto the trough of low concentrations of LiC 12 in Fig. 9b, suggesting the complementarity of these two phases through the cell, as expected.
The same behavior is also seen in Fig. 5, where the maxima of the LiC 6 concentration in Fig. 5a nearly coincide in position with the minima of the LiC 12 concentration in Fig. 5b. The complementarity of these two phases is the consequence of the binary nature of the phase diagram for the Li-graphite system after more than 50% Li is inserted per C 6 units of graphite: as the two phases undergo spinodal decomposition to their equilibrium fractions, at each states of charge the concentration of each phase is fully determined by the net Li content. As LiC 6 replaces LiC 12 across the matrix, the LiC 12 profile develops the characteristic shape shown in Fig. 9c; this shape persists during the electrode delithiation, as seen from Fig. 9c and Fig. S5 (ESI †).
Using the interpolated concentrations for LiC 6 and LiC 12 phases, in Fig. 10 we provide the extrapolated concentrations and gradients of these two phases at the electrode surface (z = 0).
The error bars of the gradients are given in Fig. S6 (ESI †). For LiC 6 , during the cell charge there is an abrupt increase of the surface concentration at % x E 0.35, as the concentration rapidly approaches unity, and it stays close to unity until discharge is initiated. The maximum gradient for LiC 6 (À0.120 AE 0.003 mm À1 ) is observed during the onset of conversion of LiC 12 to LiC 6 , when the penetration depth is small. As the LiC 6 phase spreads over preceding LiC 12 phase, the surface gradient decreases, becoming À0.012 AE 0.002 mm À1 at the peak charge. During the discharge, the decrease of the LiC 6 surface gradient continues, and at some point the gradient changes sign as the LiC 6 phase becomes depleted near the surface. As the depletion zone extends into the bulk, the gradient decreases once again. For a greater part of the cycle the highest concentration of the LiC 6 phase is at the surface. Only for % x o 0.46 during the discharge does the maximum concentration somewhat exceed this surface concentration. As seen in Fig. 5a, the formation of LiC 6 during charge and depletion of this phase during discharge are generally faster near the surface as compared to the bulk. The persistence of LiC 6 near the surface during discharge is caused by its preferential formation in this region during charge.
As seen from Fig. 9c and 10b, for the LiC 12 phase, where the maximum concentration is reached at the surface only in a narrow range of % x (0.16-0.24) which corresponds to the initial stages of LiC 12 formation near the surface. Subsequently, the maximum relocates deeper into the matrix (see Fig. S5, ESI †), as the LiC 6 phase takes over. The evolution of the gradient for LiC 12 resembles that for LiC 6 with the entire pattern shifted to lower % x. The maximum absolute gradient is observed at % x E 0.22, which corresponds to the formation of a narrow wedge of LiC 12 phase near the surface. As LiC 12 transforms to LiC 6 , the sign of the gradient changes, and it reaches a positive maximum near % x E 0.54. Subsequently it decreases (as the LiC 12 depletion zone becomes wider) only to increase again when LiC 12 becomes the main source of recovered lithium during the discharge.
Put together, our data indicate strong inhomogeneity of Li insertion and de-insertion, both in the net Li content and in the individual Li x C 6 phases.

Discussion
Previous in situ and operando approaches to visualization of Li x C 6 gradients in graphite used optical microscopy to distinguish between the colors of the lithiated grains: gold for stage I lithiation, red for stage II, and blue-grey for dilute stages. 30 This method yields qualitative insight in the succession of Li x C 6 phases, but only bands of the corresponding zones were determined. The method has particular difficulty in separating contributions from mixed phases, and it can give misleading results if the composition varies across the individual Gr particles. In our approach using X-rays, the concentration profiles of the Li x C 6 phases correspond to their bulk averages, integrating over the individual particles and quantifying the fraction of each ordered phase in these particles.

View Article Online
Presently, dynamic modeling of phase composition for individual Gr particles and the porous matrix on the whole are still in the development stages, and many aspects of phase transformations remain insufficiently understood. Bazant's phase-field periodic bilayer model appears to be particularly promising for description of stage I-stage II transitions captured in our experiments. 31 This model predicts rapid spinodal decomposition in the individual lithiated Gr particles into welldefined LiC 6 and LiC 12 subdomains which may explain why our ''mixed phase'' analysis works so remarkably well on the quantitative level. Bazant and co-workers have recently combined these models with the distributed-resistance models of the matrix to include multiple particles. 32 Another approach for describing these phase transitions combined Newman-type models with the heuristic Avrami equations for growth of the Li x C 6 phases. 33 Now, both of these approaches can be tested against the experimental data. The more traditional Newman-type models consider the Li x C 6 phases as a continuum (a solid solution, e.g., ref. 10 and 34) skipping over the details of the phase dynamics seen in our experiments. This limitation is the reason why many of our results have been presented using the net Li content of the solid matrix, which can be compared with the model simulations. The latter routinely yield sloping concentration profiles seen in Fig. 8 (e.g., ref. 35), yet for lack of observational input such models are continued to be tested and validated mainly through the electric potential measurements. Our study opens a new way in which these models can be tested, verified, and improved.
One of the less anticipated features observed in our experiments is the surprisingly long time the diffraction peaks persist in the back layer (L 4 ) during the potentiostatic hold after reaching the lower limit of 3 V (see Fig. 6), suggesting incomplete Li extraction. As seen from Fig. 5 and 6 the residual signals from LiC 6 and LiC 12 can be observed at the end of the hold period; as shown in Fig. S7 (ESI †), these signals were observed at the end of each one of the 1C delithiation halfcycles. A possible explanation may be relatively poor connectivity of some Gr particles at the end of the cell discharge, as the matrix contracts after swelling.
As mentioned in the Introduction, one of the greatest concerns with operation of LIBs at high currents is Li plating, which occurs when the rate of Li deposition exceeds the rate of Li intercalation. The latter rate is typically expressed using the Butler-Volmer equation in which the exchange current density is proportional to [(1 À x)x] 1/2 , approaching zero as x nears unity. 34 In contrast, the exchange current density of Li plating does not depend on x, so it can overtake Li intercalation in the ''red zone'' shown in Fig. 9a, where x is close to unity. This condition persists for % x 4 0.4 during charge and for % x 4 0.5 during discharge, i.e. the surface of the cell enters this perilous regime at a much lower Li content than is predicted by modeling when neglecting inhomogeneity. While the saturation of the solid matrix with Li is important for plating, equally important is the overpotential Z(x) = f a (x) À V film , where the first term corresponds to the anode potential vs. the electrolyte and the second term corresponds to the potential drop on the resistive SEI film. 34 As the current increases, so does the latter term; the overpotential becomes negative and the lithiation rate increases dramatically. Since for x 4 1/2, the potential f a (x) is small (see Fig. S8a, ESI †), even moderate currents can cause this ''thermodynamic'' Li plating condition to occur. Again, while at low current the cell average f a (x) can be close to f a (% x), when steep gradients are present (see Fig. S8b, ESI †), the front and the back of the cell can correspond to different lithiation stages, and the condition is not met uniformly across the cell. A preference for near surface Li deposition during high-current charging of the cells has been observed in the optical operando experiments of Harris and co-workers. 30 Our study suggests that due to the concentration heterogeneity Li plating can be difficult to avoid near the surface even when care is taken to keep the average lithiation sufficiently low during the rapid charge.

Conclusions
Speciation of ordered Li x C 6 phases in a porous electrode containing graphite flakes during cycling of a full cell at a (moderately high) 1C rate has been studied both in time and space using energy dispersive X-ray diffraction. The X-ray ''slicing'' of a 114 mm thick graphite electrode reveals steep gradients in the net and phase specific lithium content. The greatest inhomogeneity is observed for the LiC 6 phase. Under certain charging conditions, this phase accounts for all Li present at the surface; deeper in the electrode, the concentration exponentially falls towards the current collector. This Li inhomogeneity can have detrimental effects on cell performance, including low utilization of the active material and Li plating in the regions that are close to the electrode surface. Our data on concentration profiles in the individual phases Li x C 6 as a function of lithiation can serve as a benchmark for modeling of electrochemical processes in LIBs. While some of the features observed have been anticipated by modelers, other features are less expected, such as the surprising persistence of Li x C 6 phases during the potentiostatic hold at the end of discharge. Another peculiarity that awaits full explanation is the striking asymmetry between the charge and discharge, which suggests that the complex character of phase transitions during the high-rate delithiation may involve less ordered phases. While our method is eminently suitable to characterize phase dynamics on the scale of tens of microns, it does not provide sufficient insight into the processes occurring in the individual graphite particles, where different phase domains can coexist and affect each other. In fact, it is somewhat surprising that our analysis (neglecting such complexities) appears to adequately capture the phase dynamics under strongly nonequilibrium conditions.
To summarize, we present an experimental methodology for quantifying spatial and phase heterogeneity of lithium intercalation into graphite during rapid cycling. We hope that the insight this approach provides into electrochemical processes in practical lithium-ion cells, will spark renewed interest in validation and improvement of the cell models. In particular, a View Article Online greater emphasis on understanding intraparticle and coarsescale phase dynamics would be highly conducive to taking full advantage of this new approach.

Conflicts of interest
The authors declare no financial competing interests.