# The formulation of a CMC binder/silicon composite anode for Li-ion batteries: from molecular effects of ball milling on polymer chains to consequences on electrochemical performances

Mariama Ndour, Jean-Pierre Bonnet, Sébastien Cavalaglio, Tristan Lombard, Matthieu Courty, Luc Aymard, Cédric Przybylski, Véronique Bonnet

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## ► To cite this version:

Mariama Ndour, Jean-Pierre Bonnet, Sébastien Cavalaglio, Tristan Lombard, Matthieu Courty, et al.. The formulation of a CMC binder/silicon composite anode for Li-ion batteries: from molecular effects of ball milling on polymer chains to consequences on electrochemical performances. Materials Advances, 2022, 3 (23), pp.8522-8533. 10.1039/D2MA00702A. hal-03968700

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Submitted on 26 Sep 2024

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Cite this: Mater. Adv., 2022, 3, 8522

# The formulation of a CMC binder/silicon composite anode for Li-ion batteries: from molecular effects of ball milling on polymer chains to consequences on electrochemical performances†

Mariama Ndour,ab Jean-Pierre Bonnet, ID *a Sébastien Cavalaglio,a Tristan Lombard,a Matthieu Courty,a Luc Aymard,a Cédric Przybylski ID cd and Véronique Bonnet ID *b

The semi-synthetic polysaccharide carboxymethylcellulose (CMC) is one of the most studied and effective polymer binders for silicon-based anodes in Li-ion batteries. The formulation of the corresponding composite negative electrode with an appropriate mixture of electroactive silicon, a CMC binder and a carbon additive is mandatory to ensure a good electrical conductivity. Blending is commonly realized by a highly energetic ball milling treatment of these three aforementioned components. This type of mixing reduces the size of the obtained particles and can also potentially agglomerate them. Morever, it allows the formation of a nanostructured mixture which is essential for both the silicon activation and to achieve good electrochemical performance. However, such strong treatment can also cause a significant degradation of the polymer chains, as we have recently demonstrated for polyacrylic acid (PAA). In the present work, the structural and chemical effects of this mechanical grinding on three commercial CMCs ranging from 90 to 700 kg mol⁻¹ were investigated. All the polymers were characterized using SEC-MALLS, FTIR spectroscopy, MALDI-TOF mass spectrometry and TGA-MS thermal analysis. In all cases, a huge average molecular weight decrease was noticed, leading to the appearance of a bimodal distribution with low (52–72 kg mol⁻¹) to very low molecular weight populations (1–1.8 kg mol⁻¹). From these results, two formulations of a negative electrode were compared, one with ball milling of the three compounds and another one including only ball milling steps for silicon and carbon. After the correlation of the characteristics of this negative electrode composite with the electrochemical results, it was demonstrated that a high number of functions for supramolecular or covalent linkages are keypoints of the herein anode performance. Low molecular weight CMC derivatives (about 64 kg mol⁻¹) obtained by ball milling treatment led to higher stability of the electrode.

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Received 17th June 2022,
Accepted 22nd September 2022

DOI: 10.1039/d2ma00702a

rsc.li/materials-advances

## Introduction

In the field of lithium-ion batteries (LiBs), silicon is recognized as an anodic material of choice due to its high specific gravitational capacity of 3579 mA h g⁻¹. Such a capacity is related to the Li₁₅Si₄ phase obtained during the lithiation process and is associated with a huge volume expansion of about 280%.¹,² This volume expansion is accompanied by a drastic loss of capacity following three main phenomena which are silicon pulverization, the formation of a continuous unstable and thick layer of a solid electrolyte interphase (SEI), and even the electrical isolation of the battery after delamination of the electrode.³⁻⁵ This SEI is a passivation layer on the surface of

<footnote>a Laboratoire de Réactivité et Chimie des Solides (CNRS UMR 7314), Université de Picardie Jules Verne, 15 rue Baudelocque, 80039 Amiens Cedex, France.
E-mail: jean-pierre.bonnet@u-picardie.fr</footnote>

<footnote>b Laboratoire de Glycochimie, des Antimicrobiens et des Agroressources, (CNRS UMR 7378), Université de Picardie Jules Verne, 10 rue Baudelocque, 80039 Amiens Cedex, France. E-mail: veronique.bonnet@u-picardie.fr</footnote>

<footnote>c Sorbonne Université, CNRS, Institut Parisien de Chimie Moléculaire, 4 Place Jussieu, 75252 Cedex 05 Paris, France</footnote>

<footnote>d Sorbonne Université, Mass Spectrometry Sciences Sorbonne University, MS³U Platform, UFR 926, UFR 927, 75005, Paris, France</footnote>

<footnote>† Electronic supplementary information (ESI) available: The XRD pattern of CMC, UV traces of SEC, the FTIR spectra of CMC 250, the TGA-MS results and SEM imaging of electrodes. See DOI: https://doi.org/10.1039/d2ma00702a</footnote>
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the electrode following degradation of the electrolyte. It must remain thin and stable to allow the transport of lithium cations. To keep a good reversible capacity of silicon, the composite negative electrode must therefore present certain structural properties,⁶,⁷ such as (i) a nanoporous structure to accommodate the variation in volume during electrochemical cycling and facilitate the electrolyte diffusion, (ii) an electrically conductive network percolating through the entire electrode, to counter the low conductivity of silicon and (iii) a stable external surface of the electrode to allow the formation of a layer of the SEI, fine and stable on the surface of the silicon.

Consequently, several studies were devoted to improve the electrochemical stability by modifying the morphology of silicon,⁸⁻¹⁰ using a conductive material,¹¹ tailoring the polymer binder¹²,¹³ and also tuning the formulation parameters.¹⁴,¹⁵ For silicon-based composite negative electrodes, the choice of a polymer binder is here especially critical for the electrochemical stability of the negative electrode and, therefore, the battery.¹⁶ Here, polyvinylidene fluoride (PVDF) was one of the first investigated LiB anode synthetic polymer binders.¹⁷ However, it was observed that the resulting van der Waals interactions are not sufficient to maintain the cohesion of the electrode.¹⁸ Polyelectrolytes such as carboxymethyl cellulose (CMC) and poly acrylic acid (PAA) were then used for their carboxylic acid functions allowing substantial enhancement of electrode performance compared to PVDF. Such a kind of acidic moiety is expected to allow strengthened interactions between Si particles and polymers, by hydrogen bonding or covalent bonding.¹⁹⁻²¹ CMC (Fig. 1) is now the most widely used polysaccharide in Si-based composite electrode studies. This semisynthetic polyelectrolyte is constituted of glucose units with $β_-(1 → 4)$ linkages. The carboxymethylation is achieved by etherification of hydroxyl groups of cellulose by monochloroacetic acid.

In addition to this acidic functionalization of the polysaccharide, several polymer binder parameters can affect the stability of the anode, notably the molecular weight, the degree of substitution (DS), the polymer structure (molecular architecture) and also the type of glycosidic bonds.¹³,²²⁻²⁵ Most studies in laboratories with a Si/polymer/carbon slurry formulation use a high-energy ball-milling step in the process as “Fritsch Pulverisette” or “SPEX”¹⁹,²⁶ for mixing the materials. This milling step is needed to reduce the particle size and eventually decreases the crystallinity of the silicon to facilitate its alloying and the reversibility of the alloying.²⁷ However, on the other

<figure><img src="image_6.png" /><figcaption>Fig. 1 Chemical structure of the carboxymethyl cellulose sodium salt.</figcaption></figure>

hand, the grinding of polymers such as polysaccharides could lead to a strong degradation.²⁸⁻³⁰ Zhe Ling *et al.*²⁸ described the effects of ball milling on the structure of cotton cellulose. The authors used an Eberbach E3300 mini cutting Mill, which is considered to be a “vibratory” ball mill. They observed that the molecular weights of the cellulose samples decrease steadily with the increased milling time. Some oxidations, associated with carbonyl group amount, are also reported. Regarding crystallinity, Raman/FTIR spectroscopy studies confirm an increase of the amorphous part with the ball milling process. They suggest that cellulose crystallites are inhomogeneously perturbed during ball-milling steps leading to the so-called “inhomogeneous decrystallization”.

In the present work, we reported efforts to delineate the effect of mechanical grinding on the CMC chemical structure of the various samples and their resulting properties, in particular those involved in the stability of the negative silicon-based electrode. Particular attention was paid to investigate the impact of the most used grinding process, i.e. SPEX ball milling, on the LiB anode formulation and its consequence in the electrochemical performance of the silicon/polymer/carbon slurry composite anode.

## Results and discussion

### Silicon ball milling experiments

As a first step, 2witech silicon has been characterized by laser granulometry to determine the particle size distribution and the resulting average diameter of the particles before and after ball milling. The sample is analysed in a liquid aqueous dispersion at 0, 30 and 60 min (Fig. 2a).

We observed that, from 60 minutes, particle sizes in solution did not change anymore. A multimodal distribution was observed with 4 distinct populations of sizes around 0.3, 1, 10 and 35 µm, respectively (Fig. 2a). After grinding with SPEX for 30 min, 2 populations around 0.3 µm and 19 µm were finally obtained (Fig. 2b). The formation of these two populations confirms some results described elsewhere.²⁶,²⁷ The ball milling created the agglomeration of sub-micrometric particles. This study was carried out with a micrometric silicon of the order of 2 µm undergoing ball milling for 20 h. It is important to note that the ball milling step of Si particles exhibits a beneficial effect which is portrayed by better capacity retention. This enhanced performance is presumably due to nano-structuration thanks to grain boundary creation which leads to faster $Li⁺$ diffusion. After just 30 min of SPEX ball milling, we observed similar results to those already described in the literature.²⁶,²⁷

In addition, scanning electron microscopy (SEM) imaging of two 2witech silicon particles (before and after ball milling) allowed us to confirm the formation of agglomerates during ball milling. The images obtained at magnifications of 500 (see Fig. S1, ESI†) and 7000 (Fig. 2) show a clear difference between the pristine silicon (Fig. 2c) and the ball milled silicon (Fig. 2d). In the snapshot of commercial 2witech silicon (Fig. 2c),
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<figure><img src="image_8.png" /><figcaption>Fig. 2 Size distribution curves measured by laser diffraction granulometry of commercial silicon 2witech<sup>10)</sup> in solution at 0 min (black trace), 30 min (red trace) and 60 min (blue trace) (a) and after ball milling SPEX (b). Scanning electron microscopy (SEM) imaging of silicon before and after SPEX grinding (c and d, respectively).</figcaption></figure>

spherical particles present a very large disparity with an average size of 1–2 µm. After ball milling, we observe even larger aggregates with also a multitude of nanometric particles on the surface. These results are therefore in perfect agreement with previous ones obtained by laser granulometry (Fig. 2a and b).

## Study of the binder degradation issued from the ball milling step

Size exclusion chromatography (SEC) was used to determine the average molecular weight $\bar{M}_n$, $\bar{M}_w$ and the resulting polydispersity index ($D = \bar{M}_w/\bar{M}_n$) of different CMCs. Three commercial CMCs at 90, 250 and 700 kg mol$^{-1}$ are picked for a comparative study of the ball milling. The buffer solution (0.173 M citric acid + 0.074 M KOH pH = 3) used during SEC experiments was selected to be the closest from the reference formulation conditions. Fig. 3 shows the SEC profiles issued from the analysis of commercial and post-milled CMCs. The commercial CMC chromatograms showed a trimodal distribution with high polydispersity on different samples (Fig. 3a). This important polydispersity is well known for natural polymers. However, weight average molecular weights ($\bar{M}_w$) are fairly close to the references indicated by the manufacturer.

The comparison of the traces before and after ball milling of the three CMCs shows quasi-similar profiles for the three samples of CMC (Fig. 3b). In detail, two populations are distinguished, the first population eluted between 26 and 32 min is associated with large molecular weights (polymers).

The second population, the so-called bimodal, between 32 and 36 min, corresponds to very low molecular weights. Such results clearly demonstrate the detrimental effect of SPEX mechanical milling on the CMC structural integrity, as illustrated by the drastic reduction of apparent molecular weights. In addition to the decrease of the average molecular weight, it was demonstrated in the literature that grinding also induces a crystallinity reduction.<sup>28,29</sup>

Although, these commercial CMCs are already highly amorphous with a very low crystallinity (CrI: 17%), we observed a significant crystallinity decrease after ball milling for CMC90 and CMC250 (Fig. S2, ESI†). Table 1 shows the values of average molecular weights and the polydispersity of the different CMCs before and after ball milling.

Moreover, it was quoted out that the 2 maxima of the second population (33 and 34 min) presumably ascribed to oligomers are identical for CMC700 and 250. Surprisingly, the CMC90
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<figure><img src="image_10.png" /><figcaption>**Fig. 3** Normalized SEC-RI molar mass distribution profiles of CMC90 (blue trace), CMC250 (red trace) and CMC700 (black trace) before (a) and after ball milling (b). Samples were milled with buffer (citric acid/KOH) pH 3 and eluted in H₂O/NaNO₃/NaN₃.</figcaption></figure>

<table><caption>**Table 1** Characteristics of the molecular weight distribution of CMCs obtained from SEC before and after ball milling. $\bar{M}_w$: weight average molecular weight; $\bar{M}_n$: number average molecular weight; and $\bar{D}$: polydispersity index ($\bar{M}_w/\bar{M}_n$)</caption><thead><tr><th rowspan="2">Sample</th><th colspan="3">Commercial</th><th colspan="3">Ball-milled</th></tr><tr><th>M&#773;<sub>n</sub><br>(kg mol<sup>-1</sup>)</th><th>M&#773;<sub>w</sub><br>(kg mol<sup>-1</sup>)</th><th>D</th><th>M&#773;<sub>n</sub><br>(kg mol<sup>-1</sup>)</th><th>M&#773;<sub>w</sub><br>(kg mol<sup>-1</sup>)</th><th>D</th></tr></thead><tbody><tr><td>CMC90</td><td>9.5</td><td>124.1</td><td>13.1</td><td>2.5</td><td>6.4</td><td>2.5</td></tr><tr><td>CMC250</td><td>34.6</td><td>212.1</td><td>6.1</td><td>3.1</td><td>13.4</td><td>4.2</td></tr><tr><td>CMC700</td><td>165.6</td><td>705.5</td><td>4.2</td><td>2.9</td><td>15.0</td><td>5.0</td></tr></tbody></table>

sample did not exhibit a second peak at around 33–34 min, while the first one presents a similar intensity compared to the two other CMCs.

Another relevant point is thus that regardless of the initial molar mass of CMCs, the molar masses of populations of very low molecular weights are identical. These small molecules could thus correspond to an ultimate stage of degradation. It must be noticed here that a similar behaviour was observed

in the case of tribochemical treatments of cellulose (sonochemistry and ball milling), with the statement that degradation proceeded towards a final value, called “limiting molecular weight” ($M_{wlim}$), below which no additional chain length decrease took place, even at extended treatment times.³¹ From this result, the observed significant decrease of the polydispersity index after ball milling for CMC90 and CMC250 (from 13.1/6.1 to 2.5/4.2) and the slight increase, on the contrary, noticed in the case of CMC700 (from 4.2 to 5, respectively) can be mainly understood in terms of the relative weight important of the very narrow distribution of low molecular weight chains in regard with the larger ones. In other terms, the higher the relative percent of these oligomers, the lower the polydispersity index.

The chromatograms obtained using the UV-visible detector ($\lambda$ = 280 nm) showed the presence of carbonyl functions, for the population of low molecular weights between 32 and 36 min (Fig. S3, ESI†). In addition, no significant UV signal was detected in the large molecules corresponding to the elution time range from the chromatogram. The large molecular weights should be presumably attributed to unmodified cellulose. This mode of degradation suggests that the presence of carboxymethyl and carbonyl moieties is present within small molecular weight CMCs. A similar study carried out by Ling *et al.*²⁸ on cotton cellulose with different ball milling times revealed that the glycosidic bonds is cleaved by β-elimination on glucose residues. The formation of radicals during tribochemical treatments from milling revealed the increase of the amount of carbonyl groups. According to the authors, the more flexible C-6 groups are not really affected; therefore, this treatment does not change the amount of carboxyl groups.³¹,³²

The SPEX grinding caused an abrasion of the cell which leaves traces of iron in the final products. These traces of iron and carbon pollution avoid any clear interpretation of the NMR and RAMAN spectra, in particular to identify the presence of carbonyl groups on the milled CMC (data not shown).

The FTIR spectra of commercial and milled CMC showed infrared bands commonly observed with oxidized cellulose (Fig. S4, ESI†). Of particular interest, we can note the reduction of the OH stretching band (3600–3000 cm⁻¹) and the OH bending region (1800–1300 cm⁻¹) consecutively to SPEX treatment. The difference can be explained by the β-elimination on glucose residues of the CMC leading to carbonyl groups instead of hydroxyl groups. The drying step can also reduce the OH bending by removing the water molecules. By considering some previously described cellulose based degradation products, possible structures for them can be suggested according to the IR spectroscopy results (Fig. S5, ESI†).

Moreover, the reduction of a bending peak (around 1372 cm⁻¹), corresponding to the proportion of the crystalline part, gives additional evidence of the increase of amorphous fraction previously determined by XRD analysis (Fig. S2, ESI†).

However, it is difficult to access the exact molecular weights of the molecules obtained after grinding using SEC analysis. As aforementioned for NMR and Raman spectroscopies, ball milling is accompanied by the release of iron nanoparticles,

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<figure><img src="image_13.png" /><figcaption>b)</figcaption></figure>

<figure><img src="image_14.png" /><figcaption>c)</figcaption></figure>

<figure><img src="image_15.png" /><figcaption>d)</figcaption></figure>

<figure><img src="image_16.png" /><figcaption>Fig. 4 Negative ion linear MALDI-TOF MS spectra of the two collected SEC fractions after ball milling treatment. Detection of either ball-milled CMC 700 in the (a) high mass range and (c) low mass range or CMC 90 (b) in the high mass range (d) and low mass range (see the Experimental section for further details).</figcaption></figure>

leading to a higher chromatogram background with multi-
angle light scattering (MALS) detection. Such a phenomenon
strongly affects the possibility to obtain the accurate determi-
nation of the average molar weights. The two populations were
then separated and collected at the SEC outlet for further
characterization by mass spectrometry (MS).

The two collected fractions from SEC (large molecular
weights/small molecular weights) from CMC90 and CMC700
samples with DS of 0.7 and 0.9, respectively, were further
analysed using MALDI-TOF MS (Fig. 4). The MALDI-TOF
spectrum of CMC700 in the high mass range showed
apparent polymeric chain distributions estimated to be 52.5
and 70.93 kg mol⁻¹, for the number average molecular weight
(M̄ₙ) and weight average molecular weight (M̄w), respectively,
leading to a calculated dispersity (D) of 1.4 (Fig. 4a). As regards
the CMC90 sample, M̄ₙ and M̄w are slightly higher with 56.87
and 72.76 kg mol⁻¹, respectively. Nevertheless, polydispersity
remains close to that observed for CMC700 with D equal to 1.3
(Fig. 4b). Further examination of the spectra with optimized
settings for low mass range analysis reveals several peaks which
can be ascribed to oligo-glucosides with various degrees of
both polymerization (DP) centred at around 3–6 and up to 11,
and carboxymethylation for both CMC700 and CMC90

(Fig. 4b and d). It should also be noted that spectra are
complicated by the cation exchanges which occurred with
acidic moieties, namely H⁺, Na⁺, K⁺ and sometimes traces of
Li⁺.

Interestingly, these two analyses showed a degradation of
the native polysaccharides. Starting from a given degree
of substitution (DS = 0.7 or 0.9), ball milling with SPEX of
the CMC gives almost the same chromatogram with slightly
different size proportions. In addition, the electrode formu-
lated by this method only consists of small or even very small
CMCs regardless of the size chosen at the start (700, 250 or
90 kg mol⁻¹). It therefore does not seem very relevant to compare
these polysaccharides using this method of preparation.
To complete this study, the thermogravimetric analyses of differ-
ent CMCs were carried out at a heating rate of 5 °C min⁻¹ up to
600 °C before and after ball milling.

The TGA thermograms of both commercial and ball-milled
CMC samples are shown in the ESI† (Fig. S5). The three CMCs
exhibit a similar three-step degradation process.<sup>33–35</sup> The first
step (up to approximately 150 °C) corresponds to the loss of
bound water molecules (m = 18 g mol⁻¹) associated with the
highly hygroscopic nature of this type of polysaccharide. The
second part (between 200 and 300 °C) corresponds to a second
loss of intramolecular water immediately resulting in a rearrangement of carboxylic acid functions to anhydride with the loss of CO₂ (m = 44 g mol⁻¹). The last step corresponds to the degradation of polysaccharide chains with decarboxylation followed by chain cleavage, characterized in particular by the following mass losses (m = 12 C, m = 16 O, m = 17 OH, m = 28 CH₂ -CH₂, m = 30 g mol⁻¹ CH₂O). The comparison of the thermograms of the different CMC samples before ball milling shows a similar degradation temperature (Tonset) at 250 °C (Fig. S5, ESI†). This value at the beginning of the degradation is close to that reported in the literature (280 °C for CMC Na) for this type of cellulose with alkali cations (Li⁺, Na⁺, and K⁺).³⁶ According to the nature of the cellulose and its molecular weight, the Tonset value may present some variations. After ball milling, this temperature is lowered to around 200 °C whatever the CMC used. Such a result gives additional evidences of the presence of smaller macromolecules during grinding and it is in good agreement with the SEC and MALDI-TOF mass spectrometry results.

## Electrochemical characterization of the formulated electrode

To better assess the electrochemical performance of silicon following the addition of the polymer binder, we used two formulation methods, with CMC90 and CMC250 as polymer binders: (i) ball milling with SPEX of the Si/C/CMC powder (formulation 1) or (ii) ball milling Si/C powder with SPEX followed by magnetic stirring in a polymer suspension (formulation 2). The porosity and adhesion can give precious pieces of information on the quality of the formulation (Table 2).

The loading is preliminarily set for easier comparison of the electrochemical performances. The porosity of each electrode was calculated using the density of the different components. The porosity of the electrode obtained by formulation 2 is lower than that obtained by formulation 1 (56% versus 60% and 63% versus 69%, for CMC90 and 250, respectively). The SEM images show that such porosity comes from air bubbles due to the formulation technique but also to the presence of small cracks on the electrode (Fig. S6, ESI†). The buffer solution helps promoting adhesion to the current collector (Cu) by inducing the active corrosion of the Cu substrate and the formation of multiple strong Cu(OCO-R)₂ anchoring bonds.³⁷ The different films have fairly close adhesion, with a detachment of at least 50% of the grid surface (2B). Such an adhesion feature is suitable to efficiently perform electrochemical tests of the electrode. Only formulation 2 with CMC250 showed a lower

<table><caption>**Table 2** Surface characteristics of the different electrodes with formulations 1 and 2 in 0.173 M citric acid buffer solution (loading 1.6 mg cm⁻²; adhesion rating scale according to ASTM D3359, 5B: no peeling up to 0B: complete peeling of the film)</caption><thead><tr><td>Electrode</td><td>% porosity</td><td>pH of slurry</td><td>Adhesion</td></tr></thead><tbody><tr><td>Formulation 1 CMC90</td><td>60</td><td>3.15</td><td>2B</td></tr><tr><td>Formulation 2 CMC90</td><td>56</td><td>3.15</td><td>2B</td></tr><tr><td>Formulation 1 CMC250</td><td>69</td><td>3.15</td><td>2B</td></tr><tr><td>Formulation 2 CMC250</td><td>63</td><td>3.05</td><td>1B</td></tr></tbody></table>

<figure><img src="image_17.png" /><figcaption>**Fig. 5** FT-IR spectra of silicon powder (black trace) and mixtures of silicon with a binder (a) CMC90 or (b) CMC250 obtained by formulation 1 (red trace) or 2 (blue trace).</figcaption></figure>

adhesion at 1B compare to the other films. High porosity and low adhesion to the copper collector can cause a faster and irreversible loss of electrochemical performances.

The pH of the studied formulations (3.05–3.15) is lower than the pKₐ of carboxylic acid (4–5), allowing the functions to be kept predominantly under acidic forms to promote the reaction with the oxides of silicon.

Once the electrode film is dry, an infrared analysis is performed to determine the types of interactions involved. The spectrum of 2witech silicon is compared to those of the electrodes obtained after the two formulations used in this study (Fig. 5). In the silicon spectrum, the bands at 975 cm⁻¹ and 1202 cm⁻¹ are associated with Si-O-Si bonds due to the presence of SiO₂ on the surface of the silicon particles.

For formulation 1, the electrode analysis shows a strong band at 1604 cm⁻¹ highlighting the presence of carboxylate functions. The decrease of the band at 1202 cm⁻¹ can be associated with the modification of the silicon links, with probably Si-O-C functions. The dehydration of the electrode, after formulation 1, would potentially lead to ionic-dipole interactions.

On the other hand, the infrared spectrum (Fig. 5) of the electrode resulting from formulation 2 shows the presence of

<figure><img src="image_18.png" /></figure>
both carboxylate functions (1604 cm⁻¹), and C=O bond (1730 cm⁻¹). This last band can correspond to acid or ester functions. Karkar *et al.*²⁰ explains the presence of such a band by the formation of Si-OC(O)-R, following the esterification reaction between the SiOH group on the surface of the silicon and the carboxylic acid function of the CMC. This hypothesis suggests an influence of ionic interactions, through the carboxylate functions, but also of covalent bonds in the action of CMC as a polymer binder with this formulation.

SEM images of formulated electrodes exhibit different aspects (Fig. S6, ESI†). The electrodes obtained with formulation 2 have a heterogeneous surface with a compact appearance of the film, whereas with formulation 1, a rather smooth surface and an alveolar film were observed. The porosity is calculated by deducting the void volume after measuring the densities of the various constituents of the electrode. The electrodes obtained by formulation 2 exhibit lower porosity than those obtained by formulation 1. These results are in good agreement with the images obtained by SEM (Fig. S6, ESI†).

The formulated electrodes with CMC90 and 250 are then
cycled to compare the effect of the formulation method on the
electrochemical performance.

Electrochemical characterization of the Si/C/CMC electrode

The potential *versus* capacity curves of formulations 1 and 2 with CMC90 and CMC250 are presented in Fig. 6. All the coin cells were cycled under the same conditions for comparison purpose of the electrochemical parameters.

Here, a significantly lower first loss of capacity is system-
atically noticed for all the formulations 1 compared with all the
formulations 2 (794 and 390 for CMC90 formulations 2 and 1,
and 679 and 411 for CMC250 formulations 2 and 1,
respectively, Table 3). This result demonstrates the benefit of
polymer ball milling with C and Si onto polarization reduction
even if a drastic polymer degradation is associated with this
ball milling.

Besides, a parasitic reaction beginning at ~1 V before
the starting of the alloying reaction is noticed for both
formulations 1. More precisely, a pseudo-plateau at 0.5 V is
notified for formulation 1 with CMC90 and absent for formula-
tion 1 with CMC250. This phenomenon is surprisingly not
observed for all formulations 2. This is presumably due to the
formation of a passivation layer, which can thus be likely
related here to the reaction of the species resulting from the
CMC degradation in formulations 1. It is followed by the

<figure><img src="image_19.png" /><figcaption>Fig. 6 Electrochemical characteristics of silicon electrodes: galvanostatic curves of the first loss of capacity of the Si/Li cell in the presence of CMC90 (a) and CMC250 (c) and silicon capacity retention as a function of the number of cycles in the presence of CMC90 (b) and CMC250 (d) with formulations 1 (red trace) and 2 (black trace).</figcaption></figure>
<table><caption>**Table 3** Electrochemical data of Si/Li coin cell cycling in the presence of CMC90 and CMC250 according to the formulation method</caption><thead><tr><th rowspan="2">Formulation</th><th colspan="2">CMC90</th><th colspan="2">CMC250</th></tr><tr><th>2</th><th>1</th><th>2</th><th>1</th></tr></thead><tbody><tr><td>1st cycle coulombic efficiency (%)</td><td>77</td><td>89</td><td>80</td><td>88</td></tr><tr><td>1st capacity loss (mA h g<sup>-1</sup>)</td><td>794</td><td>390</td><td>679</td><td>411</td></tr><tr><td>1st discharge (mA h g<sup>-1</sup>)</td><td>3477</td><td>3495</td><td>3381</td><td>3459</td></tr><tr><td>30th discharge (mA h g<sup>-1</sup>)</td><td>400</td><td>950</td><td>1021</td><td>1499</td></tr><tr><td>30th discharge/1st discharge = efficiency (%)</td><td>11</td><td>27</td><td>30</td><td>43</td></tr></tbody></table>

continuous decrease of the potential which is correlated with the reaction with lithium. Bridel *et al.* suggested that this passivation layer would be formed on the carbon, thus slowing the lithium ionic conductivity and reducing the formation of the LiSi alloy.¹⁹

From a chemical point of view, formulation 1 involves the formation of oligosaccharides with low DP, predominantly between 3 and 6. These oligosaccharides could be the origin of the passivation layer on the conductive carbon. On the other hand, the absence of the pseudo-plateau for formulation 2 could be due to the conservation of the length and/or structuration of the original polymeric chains. There, the polymer could initially react with the electrolyte and therefore could prevent the formation of this passivation layer on the carbon.

Besides, a higher irreversible capacity observed in formulation 2 could be attributed to the lower mechanical cohesion of this electrode, which is in agreement with the more significant fading.

In addition, the studies of Lopez *et al.* clarify the strained aspect of polyelectrolytes, which is here due to the effect of pH on acidic functions.³⁷,³⁸ When the CMC90 sample contains a $\dot{M}_w$ of 124 kg mol⁻¹ (larger chain length), it will tend to cover a maximum of particles to allow binding where the oligomers could only cover a few particles. Improvement in capacity stability is much important with CMC250. Nevertheless, the capacity curves as a function of the number of cycles (Fig. 6b) showed better capacity retention with formulation 1.

The grinding of the composite (Si/C/CMC) by the SPEX first allows the formation of the passivation layer on the carbon. The ball-milling of CMC is at the origin of smaller chains which are more soluble in the medium allowing better formulation of the electrode.³⁹ The slurry is “smoother” allowing the electrode tape to have less visible aggregates.

Moreover, the increase of the carboxylate function content strongly supports the promotion of the capacity retention by providing more interaction sites with the surface of the silicon.²⁸,²⁹,⁴⁰ The results obtained after cycling of silicon in the presence of CMC90 or CMC250, according to the formulation method, are summarized in Table 3.

In our study, the 1st discharge capacity, less than 3500 mA h g⁻¹, is lower than the typically reported value, more than 4000 mA h g⁻¹. As the theoretical lithiation capacity is 3579 mA h g⁻¹ and that one must add to that the capacity loss in the SEI formation, about 300–400 mA h g⁻¹, one expects more than 4000 mA h g⁻¹ for a well homogenous electrode in

which the whole active mass is electronically and ionically wired. Here, the measured 1st discharge capacity values suggest that the electrodes were not well homogeneous or that there is a kinetic (polarization) limitation. The presence of CMC250 leads to the best capacity retention with an efficiency (= 30th discharge/1st discharge) of 43%, whereas a first loss of capacity of 411 mA h g⁻¹ was obtained, due to the formation of the passivation layer on the carbon. The average experimental molecular weight of CMC250 was 64 kg mol⁻¹. It has a slightly smaller average molecular weight in the case of CMC90. Keeping in mind that the starting DS for the two CMCs is 0.7, it would be expected that the electrochemical behaviour will be similar. However, the efficiency is lower in the case of CMC90, with only 27%, much lower that formulation 1.

According to our results, the adequate CMC molecular weight of the electrochemical tests seems to be around 64 kg mol⁻¹. The presence of oligomers tends to improve the formulation and allow better conductivity during cycling. However, this assumption remains to be verified and refined with further studies, especially electrochemical tests.

## Experimental

### Materials and methods

**Materials.** Carboxymethyl cellulose (CMC) sodium salt (CMC-Na) (average molecular weight = 90 000 g mol⁻¹, DS = 0.7) (CMC90), CMC250 (average molecular weight = 250 000 g mol⁻¹, DS = 0.7) and CMC 700 (average molecular weight = 700 000 g mol⁻¹, DS = 0.9) were purchased from Sigma Aldrich (Saint Quentin Fallavier, France). Silicon nanopowder (Si) was provided by 2witeck (San Diego, California). It consists of four populations of spherical particles, around 300 nm and 1, 10 or 35 µm with major volumetric mass density particles of 1 µm. Silicon has an initial SiO₂ content evaluated at 11%. Conducting additive Super C65 carbon (Cc65) was purchased from Timcal (Willebroek, Belgium). The LP30 commercial electrolyte was purchased from Merck (Schnelldorf, Germany). Fluoro ethylene carbonate (FEC), 2-(4-hydroxyphenylazo)-benzoic acid (HABA) and 1,1,3,3-tetramethylguanidine (TMG) were purchased from Sigma-Aldrich (Saint Quentin Fallavier, France) and methanol with a purity of ≥ 99.9% was from VWR (Rosny-sous-Bois, France). Ultrapure water (18.2 MΩ) and distilled water were used.

**Laser granulometry.** Determination of the various populations of spherical particles was performed before and after ball milling experiments. The distribution was estimated using a Mastersizer 3000 laser particle diffraction analyzer equipped with a Hydro EV dispersion system both from Malvern Instruments (Malvern, UK). The particle dispersion was possible with a solution of Triton X-100 (TX-100) as a dispersing agent (500 µL of 1% by weight of TX-100 in 500 ml of distilled water) at a speed of 1600 rpm with 40% ultrasound before performing measurements every 30 min at a speed of 600 rpm.

<figure><img src="image_20.png" /></figure>
**Scanning electron microscopy (SEM).** Imaging was performed using an environmental scanning electron microscope (field effect gun – FEG), model FEI Quanta200F. The samples were placed in a field with a spot at 3.5 V and a voltage of 10 kV.

**Size exclusion chromatography (SEC).** SEC experiments were performed using a LC 10 AI pump (Shimadzu, Japan) followed by an OHPAK LB-G 6B pre-column mounted in series with two LB-803 and LB-805 columns (Shodex, Germany). The detection was carried out using a RID-10A RI detector refractometer (Shimadzu, Japan) coupled with a SPD-20A UV-VIS detector spectrometer at 280 nm (Shimadzu, Japan). Light scattering measurements were performed using a DAWN8 + HELEOS II spectrophotometer from Wyatt Technology corp. (Santa Barbara, California, USA) consisting of 66 µL of K5 cell and 18 photodiodes (normalized with the detector at 90 °C using bovine serum albumin protein) and 250 of a Ga-As lasers (λ = 690 nm). The MALS instrument was calibrated using standard BSA (albumin) and pullulan (kit P-82 purchased from Wyatt technology). The analyses were performed using an H₂O/NaNO₃/NaN₃ eluent solution (18 g of NaNO₃ and 0.6 g of NaN₃ in 1 L of water), at a flow rate of 0.5 mL min⁻¹ and an oven temperature of 40 °C. CMC solutions were prepared at concentrations between 1 mg mL⁻¹ and 20 mg mL⁻¹ depending on their solubility in the eluent. 100 µL of the previously filtered CMC solution (0.2 µm, Millipore, USA) was then injected using an automatic injector (SIL – 20A, Shimadzu, Japan).

**Matrix assisted laser desorption ionization-time of flight mass spectrometry (MALDI-TOF MS).** MALDI-TOF MS experiments were performed using an Autoflex III MALDI-TOF-TOF(//TOF) or an Autoflex speed MALDI-TOF(//TOF) spectrometer (Bruker Daltonics Inc., Bremen, Germany). These instruments were equipped with a Nd:YAG SmartBeam laser (λ = 355 nm) pulsed at a 200 Hz or 1 kHz frequency, respectively. The mass spectrometers were operated in the negative ion linear mode and 2000 shots were recorded. For high mass range settings, spectra were recorded between 3000 and 150 000 m/z, with a deflection mass of 2000 and a delay of 1500 ns. For low mass range settings, spectra were recorded between 300 and 5000 m/z, with a deflection mass of 300 and a delay of 300 ns. For both settings, the following voltages are applied: 20 kV, 18.8 kV and 6.5 kV for IS1, IS2 and Lens, respectively. Mass spectra were obtained by the accumulation of 2000 laser shots and automatically processed using the Flex Analysis 3.3 software (Bruker Daltonics Inc). The instrument was calibrated using standard peptide and protein mixtures provided by the manufacturer. HABA/TMG₂ ionic liquid, used as the matrix, was prepared as described elsewhere.⁴¹⁻⁴⁴ Briefly, HABA was mixed with TMG at a 1:2 molar ratio in methanol, and the obtained solution was sonicated for 15 min at 40 °C. After removing methanol by centrifugal evaporation, the final solution was then prepared at a concentration of 90 mg mL⁻¹ in methanol, and used as a matrix without further purification. Then, 1.5 µL of the ILM was mixed with an identical volume of the aqueous sample. 1.5 µL of the mixture was spotted onto the MALDI MTP 384 polished steel plate by the dried droplet method and allowed to dry at room temperature and atmospheric pressure for 5 min.

**Fourier transformed infrared spectroscopy (FTIR).** The analyses were performed in attenuated total reflection (ATR) mode using a Shimadzu IRAffinity-1S spectrophotometer. The IR spectrum was acquired using the manufacturer software LabSolutions IR (MIRacle10 (Ge)) operating in a transmission mode with 32 scans and a resolution of 4 cm⁻¹. The field of study of the wave number σ is between 700 and 4000 cm⁻¹.

**Thermogravimetric analyses-mass spectrometry (TGA-MS).** The analyses were performed using a STA449C apparatus coupled to a QMS 403 Aeolos Quadrupole-Mass Spectrometer Netzsch (Dardilly, France). Approximately 10 mg of the sample was heated from 25 to 600 °C at 5 °C min⁻¹ under a continuous argon flow (50 mL min⁻¹).

**Electrode porosity estimation.** The porosity was calculated from theoretical calculations taking into account the electrode thickness and the different materials percentage by weight. Pycnometric densities were calculated using an AccuPyc 1330 gas pycnometer (Micromeritics, Norcross, Georgia, USA) using Helium gas. Runs were performed 5 times using a 3.5 cm³ cell. This analysis allows the determination of the density of each component of the electrode. The knowledge of the mass percentage of each element and the thickness of the electrode allows us to deduce their volume fractions. The porosity is therefore determined by deducting the volume fractions of each component of the electrode (silicon, carbon, binder, citric acid and KOH).

**Adhesion test.** The adhesion of the dry electrode layers to the copper film is determined using a base cutter (Cross Cut Adhesion Test kit CC3000, TQC). It is thus possible to have comparison values using the ASTM D3359 classification (5B: no peeling up to 0B: complete peeling of the film).

**Electrochemical characterization and electrode preparation.** Electrodes were prepared with Si/Cc65/CMC weight% formulation: 70/15/15. In all cases, the total Si/Cc65/CMC total mass was fixed at 200 mg, as 140 mg/30 mg/30 mg, respectively. A minimum of 0.5 mL of buffer solution (0.173 M citric acid + 0.074 M KOH pH = 3) was used to maintain the carboxylic functions in the acidic form. The pH of each of the formulations was measured just before spreading the mixture. The quantity of buffer could be increased to obtain a homogeneous suspension of CMC. Two formulations are studied:

(1) **Usual ball milling formulation (so-called formulation 1):** Si, Cc65 and CMC were placed with an adapted quantity of a buffer solution in a stainless-steel ball-miller jar (volume = 50 mL) with 3 stainless steel balls (10 mm of diameter) and subsequently ball milled in a high-energy (SPEX ball-miller) milling for 30 min at a frequency of 50 Hz. The resulting slurry was then coated on a 15 µm thick structured copper foil. The films were dried at room temperature overnight.

(2) **Ball milling and magnetic stirring formulation (so-called formulation 2):** Si and Cc65 were placed in a stainless-steel ball-miller jar (volume = 50 mL) with 3 stainless steel balls (10 mm of diameter). The jar was shaken in a high-energy SPEX ball-miller for 30 min at a frequency of 50 Hz. The composite
powder is added to a solution of the CMC with an adapted quantity of buffer solution and magnetically stirred in a pill for 120 min. The resulting slurry was then coated on a 15 µm thick structured copper foil. The films were dried at room temperature overnight.

No calendaring was performed on these different electrodes.

**Electrochemical characterization.** In all cases, 1 cm² disk electrodes were cut and placed in an argon-filled glovebox to be assembled in a 2035 coin-cell. One glass fiber disk (Whatman GF/D) was placed between the positive (Si/Cc65/CMC electrode) and negative (Li⁰ foil) electrodes. The used electrolyte was the commercial LP30 (1 mol L⁻¹ of LiPF₆ in EC/DMC 1/1 w/w) with 10 wt% added FEC. Cycling was performed using a Mac-Pile (Claix, France) in galvanostatic mode. The cells were cycled between 0 and 2.5 V vs. Li⁺/Li⁰ (20 °C) with C/10 (1 Li in 10 h) cycling rate and *I* = 153 mA g⁻¹ of Si.

## Conclusions

Here, we demonstrate that ball-milling has a deleterious impact on CMC samples, leading to a drastic and rapid reduction of the average molecular weight of polymers. Interestingly, regardless of the initial $\bar{M}_w$ of CMC samples, highly energetic ball milling leads, at glance, to the formation of a bimodal distribution. On the one hand, a large peak ascribed to a polydisperse high molecular weight and on the other hand two narrower ones corresponding to two low molecular weight species can be delineated. An exception is noticed for CMC90, where only one population of low $\bar{M}_w$ appears and the reason for this remains, at this stage, unfortunately unclear. These low molecular weight species presumably correspond to the final products from CMC tribochemical degradation, as already observed in the cellulose ball milling, with a “limiting molecular weight” ($M_{wlim}$), below which no supplementary polymer chain length decrease occurs.

Regarding C/Si/CMC anode formulation and electrochemical behaviour versus lithium metal, it was noticed that the electrochemical performance is slightly lower for the formulation 2 (ball milling of Si/C followed by magnetic stirring in a polymer suspension) compared with formulation 1 (ball milling of Si/C/CMC). After 30 cycles, electrochemical capacities and efficiencies are thus always superior with formulation 1 compared with formulation 2, whatever the CMC used. Coupled with this result, the 1st cycle coulombic efficiency is always higher for formulation 1 compared to formulation 2. Several assumptions are put forth such as (i) high electrode porosity. The “all SPEX” formulation including the ball milling of the polymer induces a mild porosity growth, compared to formulation 2 (60% versus 56% and 69% versus 63%, for CMC90 and 250, respectively). Grinding of all the electrode constituents, inducing a global average porosity increase, would thus facilitate electrolyte and lithium insertion. (ii) A chemical reaction between CMC and C and/or Si which may occur during ball milling and the presence of new carbonyl functions may increase interactions with Si. It would induce enhanced

electrochemical performances. These interactions would not occur if the polymer is simply added by magnetic stirring to the ball milled mixture of C and Si. A passivation layer formation during ball milling, which can likely be related to the reaction of the species resulting from the CMC degradation in formulations 1, can be mentioned. This fact is supported by the parasitic reaction at ~1 V observed in galvanostatic curves for all formulations 1 and never in formulations 2, before the alloying reaction with Si starts. This chemical reaction of the polymer during ball milling would be consequently significantly more important than the unique consideration of the CMC average molecular weight parameter. Moreover, the oligomers produced by ball milling are more soluble in the medium and, combined with the polymer, would induce a smoother and more homogeneous slurry and therefore a better formulation of the electrode. Finally, more experiments are required to discriminate the most prominent factor affecting the electrochemical performances.

## Author contributions

MN: investigation, methodology, and writing – original draft;
JPB: conceptualization, investigation, and methodology;
SC: investigation, methodology, and validation;
TL: investigation, methodology, and validation);
MC: investigation, methodology, and validation;
LA: supervision electrochemical assays;
CP: investigation, methodology, writing – original draft, and writing – review and editing;
VB: investigation; methodology; funding acquisition, project administration, resources, and writing – review and editing.

## Conflicts of interest

There are no conflicts to declare.

## Acknowledgements

Financial support from the Région Picardie and the FEDER (Fonds Européen de Développement Régional) for the NANO-PAM project is gratefully acknowledged.

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