Enhanced Performance of LiAl_0.1Mn_1.9O₄ Cathode for Li-Ion Battery via TiN Coating

Abstract

The present work addresses the issues related to the capacity fading of spinel LiMn₂O₄, such as Mn leaching and Jahn–Teller distortion and suggests an advanced TiN-coated LiAl_0.1Mn_1.9O₄ (LAMO) cathode material as an electrode for lithium-ion batteries. TiN coating layers with the same thickness but a different porosity cover the LiAl_0.1Mn_1.9O₄ electrode via reactive magnetron sputtering, and present promising electrochemical behavior. In contrast with the pristine LiAl_0.1Mn_1.9O₄, the dense TiN-coated LiAl_0.1Mn_1.9O₄ electrode demonstrates a remarkable long-term cycling by reducing the contact area of the electrode/electrolyte interface, resulting in structure stabilization.

1. Introduction

Favorable properties such as high energy density, a non-memory effect and a long lifetime [1,2] make lithium-ion batteries (LIBs) the most widely used energy storage mediums for a variety of portable power applications in everyday life. However, in order to compete with other rapidly growing technologies such as (hybrid) electric vehicles [3], there are still several issues to be solved, including the demand for higher power densities, enhanced cycle stability and safety. A great part of research worldwide is being directed to cathode development, which is the capacity-determining component in lithium-ion battery technology. From this perspective, lithium-ion cells utilizing spinel LiMn₂O₄ cathodes with a theoretical capacity of 148 mAh g⁻¹ are a good choice due to their high capacities, abundant source of manganese, low cost, low environmental impact and so on [4,5].

Despite the unique advantages, the application of LiMn₂O₄ in commercial LIBs cannot be realized since this type of electrode experiences rapid capacity fading upon cycling. The spinel material undergoes degradation attributed to the Jahn–Teller effect and Mn leaching [4,5]. A synergistic effect of these two main factors (both related to the increased content of Mn³⁺ in cathodes, as discussed below), could affect the electrochemical behavior of the cell. The Jahn–Teller distortion of Mn³⁺ ions (with electronic configuration, t_2g³-e_g¹) is associated with structural instability, especially in the 3 V region [6]. Since the diffusion rate of lithium ions in electrolytes is faster than those inside LiMn₂O₄ particles [7] at the end of discharge and especially at high current densities, lithium ions in a non-equilibrium dynamic condition accumulate at voltages >3 V first at the spinel (LiMn₂O₄) particle surface, transforming the electrode active material to Li_{1 + x}Mn₂O₄ [8,9]. The obtained Mn³⁺-rich region causes a transformation of the crystal structure on the surface of LiMn₂O₄ particles from cubic (c/a = 1) to tetragonal (c/a = 1.16) symmetry [8,10]. This can influence the three-dimensional pathways for Li ion diffusion, resulting in the capacity fading of active material [10]. In order to suppress the Jahn–Teller distortion and ensure the structural integrity of the electrode, many researchers have proposed replacing the small amount of trivalent manganese ions in the octahedral sites with several metal cations [11,12,13]. Following the same strategy, we recently studied combustion-synthesized Li_xMn₂O₄ nanostructures effectively doped with aluminium ions that minimized capacity fading and resulted in enhanced electrochemical performance, especially in comparison with undoped samples [14].

The second mechanism concerns the dissolution of Mn²⁺ in a liquid electrolyte as a result of the corrosive reaction between LiMn₂O₄ and the electrolyte, according to J.C Hunter [15]: 2Mn³⁺_(solid) → Mn⁴⁺_(solid) + Mn²⁺_(solution). This reaction dominates the end of the discharge as the concentration of Mn³⁺ species maximize. After that, the Mn²⁺ species migrate towards the anode and are reduced to metallic manganese, thereby increasing the cell impedance and influencing the solid electrolyte interface (SEI) [16,17]. At the same time, the insoluble Mn⁴⁺ ions remain on the cathode surface, which leads to severe capacity fading since they do not participate in the electrochemical reaction. The aforementioned reaction is favored using LiPF₆ as the electrolyte, as it reacts with water towards hydrofluoric acid [18,19]. Engineering the electrode’s surface using various coating technologies is an effective way to block these undesired reactions by preventing direct contact between the electrolyte and LiMn₂O₄ [20]. These coating materials include various oxides [21,22,23,24,25,26,27], active electrode materials [28,29,30], graphene [31], conductive polymers [32] and so on. Several coating technologies have been proposed to improve the integrity and uniformity of a coating layer with an uninterrupted protective layer/electrode interface and an optimum microstructure that can affect the transport of Li⁺ and e⁻, especially at high performance rates. Current technologies include chemical methods such as sol-gel [33], co-precipitation [34] and chemical vapor deposition (CVD) [35], as well as physical methods such as atomic layer deposition (ALD) [36] and physical vapor deposition (PVD) [37].

Based on previous work where the successful Al doping of spinel LiMn₂O₄ minimized capacity fading [14], we take a step forward in this study to report on the modification of the cathode surface LiAl_0.1Mn_1.9O₄ with a titanium nitride (TiN) coating layer via magnetron sputtering. Magnetron sputtering is a functional technique in which thin films can easily be obtained by carefully controlling the desired porosity and thickness. TiN compound, which has previously been applied as a coating layer for an anode [38,39,40] and an LiFePO₄ cathode [41] in LIBs, possesses excellent chemical resistance and mechanical and electrical properties [42]. Most importantly, its electrical conductivity is extremely high, ranging from 4000 to 55,500 S cm⁻¹ [43,44], depending on the crystalline quality of TiN, as well as its grain size and stoichiometry (overstoichiometric TiN_x (x > 1) can be less conductive due to Ti vacancies that act as electron recombination sites [45]). To the best of our knowledge, titanium nitride has not previously been reported as a coating material for spinel LiMn₂O₄. Herein, we study TiN-coated LiAl_0.1Mn_1.9O₄ electrodes with a common thickness but different coating material porosities. A pristine LiAl_0.1Mn_1.9O₄ electrode is also examined for comparison.

2. Materials and Methods

2.1. Materials Synthesis

LiAl_0.1Mn_1.9O₄ spinel oxide was synthesized via the combustion method described previously [46] where lithium nitrate anhydrous (LiNO₃, 99%, Alfa Aesar, Kandel, Germany), manganese nitrate hydrate (Mn(NO₃)₂∙H₂O, x ~ 4–6, 98%, Aldrich, LSC, Athens, Greece) and aluminum nitrate (Αl(NO₃)₃∙9H₂O, 98–102%, Alfa Aesar, Kandel, Germany) served as oxidizer and urea (CO(NH₂)₂, 99%, Aldrich, LSC, Athens, Greece) as fuel. The precursors were dissolved in deionized water and stirred at 200 °C, before being transferred in a muffle furnace preheated to 500 °C. The reaction took place immediately, yielding a foamy and voluminous powder. The as-prepared solids were then further calcined at 600 °C for 2 h. Details about the synthesis route have been reported in a previous work [14]. The cathode electrode was made as follows: a slurry containing LiAl_0.1Mn_1.9O₄ active material (77.5 wt.%), conductive carbon (20 wt.%) and polymer binder PVdF (2.5 wt.%) in excess of dimethylformamide (DMF) was mixed for 1 h. The blended slurry was manually brush-coated on an Al foil current collector (square sheet of 16 cm²) placed on a vacuum table and heated to 100 °C. The loading of the active material was 1 mg cm⁻².

Titanium nitride (TiN) was deposited onto the surface of LiAl_0.1Mn_1.9O₄ electrodes using reactive magnetron sputtering. For the sputter deposition, a high vacuum chamber (Pb < 5 × 10⁻⁷ mbar) equipped with a 6’’ Ti (99.999% pure) DC cathode was implemented as described in [45]. The Ar and Nitrogen flows (both 99.999% purity) were 15 and 2.3 sccm, respectively, and the target power was 450 W-DC operating in metallic reactive sputter mode. The substrate to target distance was 65 mm. The entire growth took place without intentional heating, but a macroscopic temperature up to 130 °C was recorded due to the plasma and ion bombardment. Two biasing conditions were used. In the first, the substrates were floating (self-biasing −20 V), resulting in underdense (4.3 g/cm³), porous, overstoichiometric (TiN_x > 1) and less conductive films [45,47,48,49,50,51,52] prone to oxidation [53]. Secondly, when intentional biasing V_b = −120 V was applied, the films became fully dense (5.7 g/cm³), stoichiometric, highly conductive [45,47,48,49,50,51,52] and oxidation-resistant [53]. The nominal thickness of both films was determined to be 50 nm according to the deposition rates reported in [48,49]. The reproducibility of the growth with the reported past experiments [45,47,48,49,50,51,52] was checked by comparing the spectroscopic ellipsometry spectra of old and new reference samples grown on Si in the same run with the coating of the electrodes. The surface-modified electrodes that were encoded are hereafter labeled as TiN-LAMO_50_D and TiN-LAMO_50_P in reference to the dense 50 nm TiN layer and the porous layer, respectively, while the reference electrode is noted as bare LAMO.

2.2. Physicochemical Characterization

Experimental methods for the physicochemical characterization of the synthesized materials and surfaces are described in detail in our previous works [14,46]. Powder X-ray diffraction (XRD; Bruker D8 Advance, Bruker, Birmingham, UK; Cu Ka radiation at 40 kV and 40 mA) was employed to identify the crystal structure of the electrodes. A scanning electron microscope (SEM-EDS; ZEISS EVO MA 10; Carl Zeiss SMT AG Company, Oberkochen, Germany) and transmission electron microscope (TEM; FEI Titan G2 60–300; FEI, Gräfelfing, Germany) were used to investigate the morphology of electrodes. Wide scan and core-level X-ray photoelectron Spectra (XPS) were collected using a KRATOS Axis Ultra DLD system (Kratos Analytical Ltd., Manchester, United Kingdom; monochromated AlK_α X-ray source; hemispherical sector electron analyzer; multichannel electron detector; 20 eV pass energy). A C-1s peak of contaminant carbon and an Ar-2p peak used for cleaning the surface after sputter etching were used to calculate the spectral shifts and binding energies. Spectra deconvolution was done via Shirley background subtraction, using Gaussian-Lorentzian product peaks (70% Gaussian, 30% Lorentzian).

2.3. Electrochemical Characterization

Conventional experimental procedures were applied as described previously [19,46] to evaluate the electrochemical behavior of the as-prepared electrodes at ambient conditions. Briefly, two-electrode Swagelok-type cells were assembled in an argon-filled glove box with a water concentration lower than 1 ppm, using lithium metal foil as a reference and counter electrodes and a porous inert polymer membrane (SCIMAT MG 38111; Scimt Ltd., Swindon, United Kingdom) as the separator. The electrolyte solution was composed of 1 M lithium hexafluorophosphate (LiPF₆) in ethylene carbonate (EC)/dimethyl carbonate (DMC) (1:1 in volume). The cycling behavior of the cells was studied in a Basytec multichannel battery tester (BaSyTec GmbH, Asselfingen, Deutschland) applying a potential range of 3.0–4.8 V and a current rate of 100 mA g⁻¹ (1 C = 135.5 mA g⁻¹ for LiAl_0.1Mn_1.9O₄). Cyclic voltammetry measurements were carried out in a galvanostat/potentiostat apparatus (Αutolab PGSTAT302N, Metrohm Autolab B.V., Utrecht, The Netherlands) using a scan rate of 1 mV s⁻¹ at 3.0–4.8 V. The electrochemical impedance spectroscopy (EIS) measurements were conducted at the same apparatus at a frequency range of 10⁵–10⁻¹ Hz, applying an AC amplitude of 10 mV. All potentials in this work refer to Li/Li⁺.

3. Results and Discussion

3.1. Physicochemical Characterization

The structural modifications of LAMO electrodes were studied via XRD before and after surface coating. The diffraction peaks of all samples corresponded well to the cubic spinel structure with space group Fd3m (Figure S1; JCPDS card No. 35-0782) suggesting that the addition of TiN layers did not affect the basic crystal structure of LiMn₂O₄. Crystallite sizes of spinel-based active material were calculated from line broadening of the (111) peak via a Scherrer equation, and varied in the range of 23–29 nm (23 nm for the bare LAMO material). No reflections coming from titanium nitride phase could be observed in the X-ray diffractograms due to XRD detection limitations.

TEM images were collected for the modified electrodes in order to investigate their microstructures and verify the TiN layer covering the surface of the LiAl_0.1Mn_1.9O₄ spinel. As shown in Figure 1, crystalline TiN nanoparticles were present on the surface-modified electrodes. Lattice fringes of TiN (200), (220) and (111)—with their corresponding d-spacings of 0.212, 0.150 and 0.244 nm (JCPDS card No. 38-1420), respectively—can be observed clearly in the high-resolution TEM images. In some regions, the crystalline planes (111), (220), (311) and (511)—and their corresponding interplanar distances of 0.476, 0.291, 0.249 and 0.159 nm, respectively—can also be identified, and are attributable to the LiMn₂O₄ spinel structure (JCPDS card No. 35-0782). EDS elemental mappings of selected regions of TiN-coated LiAl_0.1Mn_1.9O₄ electrodes (Figure 2) further confirm the uniform distribution of Mn, O, Al, Ti and N species, while carbon was derived from both conductive additive and graphite-coated substrate. These findings are further confirmed by XPS surface elemental analysis, as we will discuss below. The strength of the mapping trace depends on the different contents of various elements in LiAl_0.1Mn_1.9O₄ spinel particles [19].

The XPS wide scan spectra were used (Figure S2) to determine the surface elemental composition of the samples before and after electrochemical testing (Figure S3). In Figure S3a, XPS wide scan spectra indicate that the surfaces of all the studied samples (bare LAMO, TiN-LAMO_50_D and TiN-LAMO_50_P) were heavily contaminated by adventitious carbon and oxygen. It is worth noting that Mn was present in the samples even prior to electrochemical testing; we assigned it to pinholes existing in the films (i.e., the Mn originates from the substrate). The titanium nitride coated samples in Figure S3b exhibited Ti2s, Ti2p and N1s lines, suggesting the successful deposition of dense TiN and porous TiN_{x > 1} [54,55] close to equiatomic compositions. The Ti2p_3/2 line is a sensitive probe of the oxidation state and stoichiometry of titanium in titanium nitride [56,57]. The Ti2p_3/2 spectra exhibited a fine structure that was attributable to the different phases and oxidation states of Ti in TiN and the relevant compounds indicated in Figure S3c. In particular, the lowest energy peak can be assigned to stoichiometric TiN [54,55], the peak at 456.3 eV to over-stoichiometric TiN_x [58], the peak at 458 eV to TiO_xN_y [59] and, finally, the peak at 459.2 eV to TiO₂ [60].

3.2. Electrochemical Characterization

The electrochemical characterization of the pristine and TiN-coated LiAl_0.1Mn_1.9O₄ electrodes was carried out with galvanostatic charge-discharge measurements at room temperature. Figure 3a shows the cycling performance of the electrodes at 100 mA g⁻¹ in the potential range of 3.0–4.8 V, while Figure S4 provides the Coulombic efficiency [61] of the cells during the first cycle. The bare LAMO, TiN-LAMO_50_D and TiN-LAMO_50_P electrodes exhibited initial discharge capacities of 109.8, 104.7 and 100.0 mAh g⁻¹, respectively. However, after the long-term operation of 400 cycles, the surface-modified electrodes showed a remarkable stability compared to the bare LAMO. Indeed, the bare LAMO, TiN-LAMO_50_D and TiN-LAMO_50_P delivered 37.3, 76.3 and 60.7 mAh g⁻¹ (maintaining 34%, 72.9% and 60.7% capacity retention), respectively, after 400 cycles. It should be noted that the dense TiN layer affected the charge/discharge process in a more positive way, resulting in an enhanced cyclic stability compared to the porous layer. The charge-discharge profiles of the samples during the first and 400th cycle are shown in Figure 3b. As can clearly be seen, the bare electrode suffered from faster capacity fading due to degradation of the spinel nanoparticles (as demonstrated in the literature). The charge-discharge plateaus related to the lithium-ion insertion/extraction stage completely disappeared after 400 cycles in contrast with the covered electrodes, confirming the protective role of titanium nitride deposition in active material stabilization. Figure 3c displays the rate behavior of the bare LAMO and TiN-LAMO_50_D for current densities ranging from 200 to 800 mA g⁻¹ in the potential window of 3.0–4.8 V. The coated electrode behaved with superiority to the pristine electrode when cycled under the same current rate. Interestingly, the bare sample provided almost 75 mAh g⁻¹ when the rate returned to 200 mA g⁻¹, while the surface-modified electrode delivered the same capacity for the double current rate. The Coulombic efficiency of TiN-LAMO_50_D was almost 100% for 250 cycles at different current rates, in addition to a significantly enhanced rate performance. The promoted performance of the modified electrode can be ascribed to (i) increased conductivity, which promoted a faster electron transport between the LiAl_0.1Mn_1.9O₄ particles, and (ii) protection against manganese dissolution. Both of these achievements resulted from the TiN coating layer.

To obtain more insight into the active electrochemical surface area of the bare and surface-coated LiAl_0.1Mn_1.9O₄ electrodes, cyclic voltammograms were collected in the potential range of 3.0–4.8 V. Generally, LiMn₂O₄ spinel materials show double oxidation and reduction peaks, which reflect the stepwise process of lithium ion insertion/extraction into the spinel structure [19,46,62]. Figure 4 displays the CV curves during various cycles. Apparently, the overlapping of the two characteristic peaks associated with Li ion insertion/extraction is related to limited lithium-ion diffusion at elevated scan rates [46]. Among the samples tested, TiN-LAMO_50_D showed the highest electrochemical surface area, as obtained from the various peaks. It is believed that the improved conductivity of an electrode with a dense TiN coating of 50 nm could allow for faster electrochemical reaction kinetics. Both types of peak decreased faster in the unmodified electrode, as compared with the rest of the samples. This is strong evidence of spinel protection and the improved reversibility of surface-coated electrodes. Moreover, the peak positions of the pristine LiAl_0.1Mn_1.9O₄ electrode were significantly shifted as cycling continued. Consequently, higher oxidation and lower reduction potentials indicate the potential for a higher polarization of a bare LiAl_0.1Mn_1.9O₄ electrode, which was induced by the lower electronic conductivity of this sample [19,46]. These findings reveal that spinel structures were more stable during the charge/discharge process and suppression of Mn dissolution in the surface-modified electrodes, which could partly explain the enhanced cycling stability.

EIS measurements were recorded for all the samples in order to shed light into the processes taking place in bare and modified electrodes at a discharged state (3.0 V) cycled under a 100 mA g⁻¹ current rate. Nyquist plots of the electrodes after 200 and 400 cycles are shown in Figure 5, along with the equivalent circuit used to simulate the experimental data. The values of the fitted resistance parameters are listed in Table S1, and the corresponding fitting curves are presented in Figure S5. After prolonged cycling (from the 200th to 400th cycle), the measured impedances R_f and R_ct show an increasing trend for all the samples that resulted from the extended surface passivation and degradation of spinel particles. Table S1 shows that the increase of R_f from the 200th to 400th cycle was significantly lessened in the surface-modified electrodes with the following trend TiN-LAMO_50_D < TiN-LAMO_50_P, as compared to the bare one. The film resistances defined the long-term operation of electrodes, since the lower values of R_f led to enhanced capacity retention and, ultimately, the protective layer suppressed the formation of the passivation layer on the electrode surface. After the 400th discharge, the TiN-LAMO_50_D electrode exhibited the smallest R_ct (31.5 Ω) among the other samples, indicating a facile Li⁺ transport due to the effective surface stabilization from the dense 50 nm protective layer.

The lithium-ion diffusion coefficient D_Li+ can be calculated by the following equations [63]:

$${\mathrm{Z}}^{\prime }={\mathrm{R}}_{\mathrm{f}}+{\mathrm{R}}_{\mathrm{ct}}+{\mathsf{\sigma }\mathsf{\omega }}^{-0.5}$$

(1)

$${\mathrm{D}}_{{\mathrm{Li}}^{+}}=\frac{{\mathrm{R}}^2{\mathrm{T}}^2}{2{\mathrm{A}}^2{\mathrm{n}}^4{\mathrm{F}}^4{\mathrm{C}}_{\mathrm{Li}}^2{\mathsf{\sigma }}^2}$$

(2)

where Z′, ω, R, T, Α, n, F and C refer to the real part of the impedance, the angular frequency in the low-frequency region, the gas constant, the absolute temperature, the contact surface area between electrode and electrolyte, the number of reaction electrons per molecule during oxidization, the Faraday constant and the molar Li⁺ concentration in the electrolyte, respectively. Moreover, σ represents the Warburg factor, which is relative to Z′ (Equation (1) and can be obtained from the slope of the linear relationship between Z′ and ω^−0.5 in the low-frequency region (Figure 6)). The calculated lithium-ion coefficient values of the bare LAMO, TiN-LAMO_50_D and TiN-LAMO_50_P after 400 cycles were 5.24 × 10⁻¹⁴, 1.79 × 10⁻¹³ and 1.25 × 10⁻¹³ cm² s⁻¹, respectively. The TiN-LAMO_50_D electrode possessed the highest D_Li+, indicating an enhanced Li⁺ transfer believed to be a consequence of the stabilized surface and structure provided by the TiN coating.

3.3. EDS/XPS Analysis after Cycling

Post-mortem analysis of the cycled TiN-LAMO_50_D electrode via SEM/EDS (Figure S6) revealed that this electrode contained more manganese as compared to the uncoated LiAl_0.1Mn_1.9O₄ electrode, demonstrating the strong shielding effect of titanium nitride deposition against manganese dissolution in the electrolyte, which clearly explains the large difference of capacity retention observed in Figure 3a.

XPS after electrochemical testing suggested that all surfaces were enriched with F (Figure S3). The TiN-LAMO_50_D sample successfully endured electrochemical testing, and Ti and N were still present in the wide scan spectra (in Figure S2) along with the Ti2p_3/2 core levels (in Figure S3c) that resulted from significant contribution to the surface composition, according to Figure S3a. On the contrary, the TiN-LAMO_50_P sample showed a substantial removal of Ti from the surface to the verge of elimination, both in the wide scan spectra (Figure S2) and the Ti2p_3/2 core levels and total oxidation of any Ti-remnants to form TiO₂ (Figure S3). The Mn2p_3/2 core level (Figure 7) spectra provide further relevant insights. The LAMO sample exhibited an exclusive peak of Mn2p_3/2 with an energy-binding characteristic in the spinel LiMn₂O₄ (Figure 7) [64]. After electrochemical testing, there was a strong evidence for the existence of MnO₂ [65] on the surface of the LAMO, and a potential indication of the formation of MnO via the existence of a characteristic satellite peak at 646 eV [65]. It has to be noted that this peak was accompanied by a dominant satellite peak of MnO at around 641 eV [66]. Thus, the Mn2p_3/2 core levels were deconvoluted to contributions of Mn for valence II, III, IV, VI and VII (note that the valence VII peak overlaps with the satellite of valence II) according to [66], as shown in Figure 7a; the results of the deconvolution are summarized in Figure 7b. Before cycling, the Mn in the TiN-LAMO_50_D and LiAl_0.1Mn_1.9O₄ samples was mostly present in valence IV (MnO₂), while it decreased in the dense electrode and remained intact in bare LAMO after the electrochemical testing. On the contrary, the Mn in the TiN-LAMO_50_P sample was mostly present in valence III, suggesting that the deposition of TiN_x promoted surface defects on the LiAl_0.1Mn_1.9O₄ substrate. Moreover, before electrochemical testing, Mn²⁺ could be observed in the TiN-LAMO_50_D, despite the fact that only valences III and IV were supposed to be detected in fresh spinel material. The lower average oxidation state might be associated with the minimal removal of oxygen atoms from spinel material during the sputtering process. This could be more intense in the case of a dense coating layer, depending on the different deposition conditions of the two samples, as previously discussed. After electrochemical testing, the LAMO sample did not show any significant valence difference, while the Mn in TiN-LAMO_50_D switched mostly to valence III (from valence IV). On the contrary, TiN-LAMO_50_P switched from valence III to valences IV and VI, which resemble the bare LiAl_0.1Mn_1.9O₄ sample, and thus this might have been the result of the removal of TiN_x from the LiAl_0.1Mn_1.9O₄ surface, exposing the underlying LiAl_0.1Mn_1.9O₄ itself. It is evident that the TiN-LAMO_50_D sample was superior to the TiN-LAMO_50_P in terms of its durability in the electrochemical test, which is in accordance with its high density (5.7 g/cm³) [46] and hardness (24.5 GPa) [47].

4. Conclusions

Titanium nitride coatings of the same thickness but with different porosities deposited onto the surface of LiAl_0.1Mn_1.9O₄ electrodes proved capable of enhancing the cathode performance in a LIB cell by protecting and stabilizing the spinel material. The dense TiN-coated electrode was the most beneficial approach, leading to superior capacity retention, while the uncovered electrode showed severe capacity fading, implying faster spinel degradation. The effectiveness of the dense TiN layer compared to the porous one is estimated to have resulted from the better metallic behavior of the former, promoting the electron transport to the inner active material and thus allowing for faster electrochemical reaction kinetics. CV measurements confirmed the improved reversibility for surface-coated electrodes while EIS data accompanied with the calculated lithium-ion coefficient values revealed the enhanced Li⁺ transport promoted by the protective layer. XPS confirmed the removal of the porous TiN_x layer from the LiAl_0.1Mn_1.9O₄ surface, while the dense TiN layer remained intact after the electrochemical measurements. In the latter case, a slight removal of oxygen atoms from the spinel framework during the TiN sputtering process cannot be excluded, as indicated by the existence of Mn²⁺ before the electrochemical testing. As for the bare LiAl_0.1Mn_1.9O₄ electrode after the long-term operation, there is strong evidence of the existence of MnO₂ and a potential indication of the formation of MnO, implying a cause of disproportional reaction where Mn⁴⁺ ions remain on the cathode surface and lead to severe capacity fading. This research enables the design of new cathode electrodes utilizing protective layers against side reactions, showing promising behavior for next-generation LIBs.