NCA, NCM811, and the Route to Ni-Richer Lithium-Ion Batteries

Abstract

The aim of this article is to examine the progress achieved in the recent years on two advanced cathode materials for EV Li-ion batteries, namely Ni-rich layered oxides LiNi_0.8Co_0.15Al_0.05O₂ (NCA) and LiNi_0.8Co_0.1Mn_0.1O₂ (NCM811). Both materials have the common layered (two-dimensional) crystal network isostructural with LiCoO₂. The performance of these electrode materials are examined, the mitigation of their drawbacks (i.e., antisite defects, microcracks, surface side reactions) are discussed, together with the prospect on a next generation of Li-ion batteries with Co-free Ni-rich Li-ion batteries.

1. Introduction

Major challenges of the 21st century concern the global climate change and dwindling fossil energy reserves that motivate the scientific community to develop sustainable solutions based on renewable sources of energy, which require accumulators to store electricity, i.e., rechargeable (secondary) batteries. Since their first commercialization in 1991 by Sony Corp., lithium-ion batteries (LIBs) have penetrated the mass market as power sources. The reason of this success is explained by the performance of the Li-ion battery technology. Depending on the choice of the electrodes, the volumetric energy density of LIBs is in the range 200–350 Wh L⁻¹ and on average the gravimetric density is 150 Wh kg⁻¹. This outperforms the other electrochemical batteries (Pb-acid, Ni-Cd Ni-MH). For some applications, these other batteries are still of interest because they are less expensive. However, the choice of Li-ion is mandatory when higher energy and power densities are needed. Such is the case when volume is a key parameter: batteries for phones, cameras, computers for instance. This is also the case when both energy density and volume densities are important parameters, such as batteries for electric vehicles. Other current applications concern batteries used to solve the intermittence problems of the electricity produced by wind or photovoltaic plants, more and more developed as renewable energy sources, and considered as the only solution to give access of electricity to the sub-Saharan countries in Africa. The initial LIB chemistry consisted of lithium cobaltate LiCoO₂ (LCO) as positive electrode (cathode) and carbon (graphite) as negative electrode (anode) in between of which a separator soaked with an organic electrolyte (ionic conductor) [1]. Now, the energy density of LCO-based LIBs has reached the value of 280 Wh kg⁻¹ (700 Wh L⁻¹) [2], which explains that LCO still occupies most of the market in the field of portable electronics.

The main drawback of all the cathode materials in such batteries is the limited rate capability because of a low ionic and/or electronic conduction [3]. The sluggish kinetics impose the fabrication of redox-effective particles as small as possible to reduce the diffusion path length of the lithium inside the particles. That is why many efforts have been made to reduce their size to the nanoscale. The electrode material performance reached today is above all the benefit of the progress in nanoscience. Okubo et al. [4] have observed an increased rate capability of LiCoO₂ when the size of the particles was reduced to 17 nm, with a capacity delivered at 100 C as high as 62.5% of the capacity at 1 C.

LCO presents the disadvantages of high price, cobalt toxicity and a rather small capacity (≈140 mAh g⁻¹) due to oxygen loss in the partially delithiated Li_1−xCoO₂ cathode (x ≈ 0.5). For these reasons, in addition to safety issues, LCO cannot be used as power supply for electric vehicles (EVs). Increase of the driving range of EVs is needed to increase the market of EVs and replace the petrol cars by EVs to meet the ambitious goal of reduction of CO₂ emission (95 g_CO2/km mandated by E.U.) [5]. The energy density E must satisfy the relation E = QV, which imposes high operating cell voltage (V) and large stored capacity (Q) delivered to loads. High cell voltage can be obtained using an anode material with a potential close to that of Li metal (3.04 V vs. standard hydrogen electrode (SHE)) and a high-voltage cathode (>0.5 V vs. SHE); moreover, according to the Faraday law (Q = nF/M_w), the capacity is determined by the number of transferred electrons (n) and the molar weight of the active electrode material (M_w). Since it is difficult to avoid the use of graphite as an anode, for reasons discussed elsewhere [3], the most feasible method involves an increase of the capacity and working voltage of the cathode. Various compounds with two- and tri-dimensional structures have been intensively investigated as cathode materials: LiCoO₂ (LCO), LiMn₂O₄ (LMO), LiFePO₄ (LFP), LiNi_xCo_yMn_zO₂ (NCM), and LiNi_xCo_yAl_zO₂ (NCA) with x + y + z = 1 [2,3]. Among them, two Ni-rich layered oxides, LiNi_0.8Co_0.15Al_0.05O₂ (NCA) and LiNi_0.8Co_0.1Mn_0.1O₂ (NCM811) are increasingly popular active cathode elements used in commercial LIBs for electric cars and planes. The first reason is that the redox activity of nickel occurs at higher potential vs. Li⁺/Li than iron in LFP or Mn in LMO. This composition LiNi_0.8Co_0.15Al_0.05O₂ for the NCA material imposed itself because it is less expensive and is more environmentally benign than other compositions [6,7,8]. On another hand, Li[Ni_xCo_yMn_z]O₂ has been investigated at different Ni concentrations since, the early works of Ohzuku’s [9,10] and Dahn’s [11,12] groups, with focus on x:y:z = 5:3:2 (NCM532), 6:2:2 (NCM622), and 8:1:1 (NCM811) for applications requiring high density. The larger Ni fraction, the higher energy density, since Ni is the redox-active element both in NCA and NCM. This increase in Ni concentration, however, is accompanied with a decrease in structural and thermal stability due to the weaker Ni-O bonds, and thus a decrease in cycling ability. In addition, the chemical reactivity of the surface layer is increased due to the more oxidizing Ni³⁺/Ni⁴⁺ redox potential. The degradation mechanisms for all the ternary Ni-based cathode materials at high voltage have been discussed by Zhang et al. [13]. Surface modification of the Ni-rich materials is the standard process used to improve the structural stability and protect the cathode element against side reactions with the electrolyte. This will be reviewed below. However, this process presents some drawbacks for Ni concentrations larger than 0.8 [14,15]. Homogeneous coating often requires a wet-coating process using a liquid. However, the surface is altered in the process, because the liquid medium reacts with Ni³⁺ to form impurity compounds, which degrades the electrochemical properties when the Ni concentration is too large, in practice when x > 0.8. Other methods, including chemical vapor deposition (CVD), atomic layer deposition (ALD) can be used to obtain homogeneous coatings, but they are expensive and not viable from a commercial point of view. Moreover, the problem of microcrack generation and subsequent electrolyte infiltration, which decreases the cycling life, is a major problem for x > 0.8. The compromise for practical use of these N-rich cathodes is currently a Ni concentration x = 0.8, even though we shall comment on the recent progress to overcome this difficulty. That is why the interest in this work is focused on NCM811 that has this fraction of nickel, the same as that of NCA. In practice this is the highest Ni concentration that can be used, because NCM with higher Ni concentration (like NCA) suffer from their low cycling stability [16]. This is illustrated in Figure 1. The degradation of Ni-rich NCM and NCA materials with different compositions was addressed by Sun et al. [17].

The aim of this article is to examine these two advanced cathode materials for EV Li-ion batteries that are already commercialized as lithium-ion batteries in the electric vehicle market [18,19]. Both materials have the common layered (two-dimensional) crystal architecture isostructural with LiCoO₂.

As we mentioned, nanosized particles have major advantages. In addition, nanosized particles can accommodate the volume change during cycling while microcracking occurs during cycling, which nucleate preferentially at the grain boundaries. Therefore, single crystallized particles, which can be synthesized only at the nanoscale, minimize the risk of microcracking responsible for a shortage of the cycle life in the materials considered in this review [20]. In practice, however, it is difficult to use monodisperse particles of a nanosize. First, smaller particles tend to agglomerate, and nanopowders are difficult to handle at the industrial scale. Moreover, commercial cathodes contain a mix of large and small particles, which is needed to increase the packing density. However, the presence of the smaller particles is always needed to insure a good electrochemical performance. Smaller particles also means increased effective surface between the cathode materials and the electrolyte, thus raising the problem of the side reactions at the cathode–electrolyte interface (CEI). As we shall see, the control of the CEI is the major difficulty met with the Ni-rich materials, together with the formation of microcracks during cycling that favor the penetration of the electrolyte to form insulating CEI limiting cycle life of the batteries. In this work, we review the solutions that have been found to overcome these difficulties, opening the route to a new generation of LIBs with enhanced energy density. After a brief description of the structural characteristics, we report some electrochemical properties to highlight the performance of these electrodes, and review the state-of-the-art in the methods of atomic doping and surface coating to improve the limited cycle ability and rate capability of the NCA and NCM cathodes.

2. Structure of Layered Lithiated Oxides

Lithium transition-metal (TM) oxides LiMO₂ (M = Co, Ni, Mn, Cr) crystallize in the α-NaFeO₂ structure belonging to R3¯ m (D_3d⁵) space group (S.G.). The same holds true for their related oxides LiCoM’O₂ where M’ is a divalent or trivalent substituting ion. In this lattice, the Li⁺ ions are stacked between MO₂ slabs. [21]. The octahedra are face-sharing. These oxides show high operating voltage > 3 V vs. Li due to the d-electron character of TM. LiN_1−yCo_yO₂ solid solutions belong to this family, and exist in all proportions between LiNiO₂ and LiCoO₂, because the radius of Co³⁺ ion (r_Co³⁺ = 0.545 Å) is almost the same as that of Ni³⁺ ion (r_Ni³⁺ = 0.56 Å) in octahedral site [22]. Schematic crystal structure of O3-LiMO₂ is shown in Figure 2. The “O3” label indicates that the Li environment is octahedral with ABCABC stacking order of the oxygen layers. As a result, the hexagonal unit cell includes three sets of Co and Li layers.

LiNiO₂ (LNO) cannot be an alternative to LCO, because of the cation mixing (CM), that is the migration of Ni ions from the intralayer plane (3a sites) to the Li plane (3b sites) [23]. This CM reduces the electrochemical performance and can lead to subsequent modification to spinel (cubic) structure. Three ways have been successful to minimize the CM. The first one is the optimization of the synthesis process and synthesis parameters in Li_1−xNi_1−yCo_yO₂ [24]. This material does not show any loss of oxygen until x = 0.3. In LiNi_1/3Mn_1/3Co_1/3O₂, a solid solution of LiNiO₂-LiCoO₂-LiMnO₂, the cation mixing between lithium and nickel on the 3b Wyckoff site implies that the chemical formula can also be written under the form [Li_1−yNi_y]_3b[Li_x+yNi_{(1−x)/3−y}Mn_(1−x)/3Co_(1−x)/3]_3aO₂ (x = 0.01, 0.04). Mn atoms are introduced in these materials to increase the structural stability. The second process to minimize the cation mixing is the partial substitution of aluminum for nickel. Recently, Nie et al. found a third process to minimize the cation mixing in NCA is the calcination of the material under an oxygen pressure of 0.6 MPa [25]. In LiNi_0.8Co_0.15Al_0.05O₂, Al³⁺ cations (r_Al³⁺ = 0.53 Å similar to Ni³⁺ and Co³⁺) occupy the TM sites in the layered R3¯ m crystal structure [26].

3. LiNi_0.8Co_0.15Al_0.05O₂ (NCA) 3.1. Synthesis

Among the Ni-rich layered compounds, LiNi_1−y-zCo_yAl_zO₂ demonstrates superior electrochemical performance with respect to non-Al doped mixed LiNi_1−yCo_yO₂ materials owing to its structural and thermal stability [27,28]. Even though this electrode suffers from the serious side reactions with electrolyte and HF erosion, which reduces its cycle life, the particular composition LiNi_0.80Co_0.15Al_0.05O₂ is now used as the cathode in the 100-kWh battery pack of the Tesla EV Roadster by Tesla [29]. NCA-based batteries are also used by SAFT for various applications [30]. Majumdar et al. [31] used aluminum nitrate and metal acetates to prepare NCA via wet-chemical route. As a cathode, this powder cycled in the potential range 3.2–4.2 V delivered a capacity of ≈136 mAh g⁻¹ at a current density 0.45 mA cm⁻². NCA was also synthesized via a coprecipitation route with less than 1% antisite defects (Ni on Li sites) [32]. Usually, the coprecipitation method uses NH₃H₂O as the chelating agent, which produces by-products causing serious pollution problems. More recently, good results were obtained by using a different chelating agent, namely ethylenediaminetetraacetic acid (EDTA) [33]. Ropelike NCA fiber was prepared via electrospinning and sintering. As a cathode, it delivered a capacity of 206.4 mAh g⁻¹ at 0.1 C, and maintained 75% capacity retention after 100 cycles at 1 C [34]. A green and low-cost synthesis of NCA was also proposed, by using C₄H₄O₆KNa·4H₂O as a chelating agent to prepare Ni_0.80Co_0.15Al_0.05(OH)₂ used as the precursor obtained through a coprecipitation method using potassium sodium tartrate [35]. Wu et al. used SiO₂ hollow nanospheres as hard template to synthesize LiNi_0.80Co_0.15Al_0.05O₂ hollow nanospheres with a diameter of about 1.8 μm (NCA HNSs). The NCA HNSs exhibited a reversible capacity of 202.4 mAh g⁻¹ at 0.1 C and 179.1 mAh g⁻¹ after 80 cycles at 1 C rate [36]. LiNi_0.80Co_0.15Al_0.05O₂ was also recently synthesized via flame-assisted spray pyrolysis method as sui economical alternative in NCA mass production [37]. Such NCA particles showed the initial specific discharge capacity of 143 mAh g⁻¹, and the capacity retention of 92% after 20 cycles. Indeed, the capacity outperforms that of commercial NCA available on the market (138 mAh g⁻¹). NCA prepared by using N-methyl-2-pyrrolidone (NMP) and urea-based solvothermal reaction exhibited a capacity of 203 mAh g⁻¹ at 0.1 C, and most of all excellent rate capability (117 mAh g⁻¹ at 10 C, 74.4% capacity retention at 300^th cycle) attributed to enhanced exposure of {010} planes [38].

3.2. Degradation Mechanisms

Bang et al. [39] investigated the thermal runaway of the delithiated cathode. The XRD spectra were recorded at different states-of-charge (SOCs). When the SOC increases, an increase in the distance between (018) and (110) Bragg lines at 2θ = 65° is observed, which gives evidence of an increase of the c/a ratio in NCA [40]. The main problem to be solved with LiNi_0.80Co_0.15Al_0.05O₂ cathode is the rapid degradation upon cycling due to the well-known phase transition from a layered structure (R3¯ m) to disordered spinel (Fd3m) which then transforms to the NiO-like rock-salt structures (Fm3m) in the surface layer [41,42,43,44,45,46,47,48,49,50]. This structural transformation is due to the strongly oxidizing Ni^3+/4+ ions interacting with the electrolyte in the surface layer. It results in the formation of a resistive cathode–electrolyte interface and leads to loss of capacity and an increase of the impedance for Li⁺ diffusion [51,52,53] and a fatigue of the material [54,55,56]. Moreover, surface reconstructions occurring at charging voltages > 4.3 V or cycling above 40 °C trigger release of oxygen responsible for exothermic reactions with organic electrolytes [57,58,59,60,61,62] and thermal runaway [63,64]. In addition, Ni-rich materials undergo multiple phase transitions during cycling according to the sequence H1→M→H2→H3, where H1 is the layered structure, M a monoclinic phase, while H2 and H3 are hexagonal phases. The H2→H3 phase transition occurs at ≈4.2 V for Ni concentrations larger than 80 atomic % Ni cathodes, and creates crack networks throughout the secondary particles of NCA [65], and NCM as well [66]. These crack networks along the grain boundaries are infiltrated by the electrolyte, resulting in the formation of an insulating NiO-type cathode–electrolyte interface [67,68]. Belharouak et al. [69] studied the thermal degradation of de-intercalated NCA samples. The authors reported that the oxygen release in the delithiated state was linked to several structural phase transitions, ranging from a Rm→Fd3m (layered→spinel) transition to a Fd3m→Fm3m (spinel→NiO-type) transition. Using solid-state NMR spectroscopy, Leifer et al. [70] monitored the electrochemical properties of NCA cathode cycled in different voltage windows. When charged to lower voltage, a more complete lithium intercalation was achieved upon discharge due to the return of the environments of Li⁺ and Al³⁺ in their initial configuration. These results illustrate that the capacity of this material is heavily dependent on the stability of its lamellar structure. Indeed, the Al³⁺ ions in NCA travel easily into the lithium layer [71], which prevents the material from collapsing into a NaCl phase [72]. The drawback, however, is that Al³⁺ ions also accelerate the spinel transformation [73]. Using transmission electron microscopy and electron diffraction, Zhang et al. investigated the structure evolution induced by the layered→spinel phase transformation at the atomic scale [74]. They considered NCA cathode particles charged to 4.7 V and observed the formation of a core–shell structure generated by the layered→spinel phase transformation. The layered→spinel phase transformation issues from the migration of transition metal ions from the 3a layered sites to the 4d spinel sites. This migration follows a 5-step pathway proposed by Guilmard et al. [75] and analyzed by Kim et al. [76]. The intermediate spinel phase is nucleated first; then spinel domains are formed, which grow up to the formation of the complete spinel structure. Simultaneous measurements including both the structural changes and the kinetic process revealed that such structural changes are accompanied with high kinetic barriers for Li-ion extraction [77]. Recently, X-ray coupled scanning tunneling microscopy measurements revealed that the nickel ions are predominantly Ni^II in the first atomic layer and mixtures of Ni^II with Ni^III/Ni^IV already appearing 1.5 nm into the NCA particle. These results reveal the interplay between irreversible surface transformations and the bulk reactions [78]. One of the causes for the short cycle life is the release of Ni²⁺ ions from the LiNi_0.8Co_0.15Al_0.05O₂ cathode and the formation of Ni-metal particles at the surface of the graphite anode [79]. Therefore, this material, as any active cathode element, requires the coating of the nanoparticles with a layer to protect them from side reactions with the electrolyte, prevent the loss of oxygen, avoid the dissolution of the transition metal ions in the electrolyte, and stabilize the surface layer [80].

3.3. Stability Improvement

3.3.1. Coating NCA

One of the first coating materials explored for NCA is carbon [81]. Many efforts have been made since then to explore different coatings. Fluorine has been used under different forms to modify the surface of NCA. Since it is more electronegative than oxygen, fluorine can substitute to oxygen and generate stronger metal-fluorine bonds, which not only enhances the stability of the lattice, but also protects the cathode material from HF or nitrogen attacks [82]. Surface-fluorinated LiNi_0.80Co_0.15Al_0.05O₂ delivered a capacity of 220 mAh g⁻¹ with capacity retention of 93.7% after 80 cycles at 0.1 C, owing to the partial replacement of the metal–oxygen bond by the stronger metal–fluorine bond that stabilized the structure [83]. A dry and low-temperature fluorination (350 °C) method was proposed by Zhao et al. [84]. The sample fluorinated with 1 mol% F exhibited a capacity retention of 93.9% after 100 cycles at 1 C, against 86.2% for the pristine sample. It was argued that the fluorination generates amorphous LiF coating layer on the particle surface, thus restraining the diffusion of metal ions conveyed in the electrolyte. AlF₃-coating was proposed by Lee et al. [6]. More recently, electrochemical and thermal properties of NCA were also improved by coating with FeF₃ [85]. The FeF₃-coated NCA cathode delivered a capacity of 182.2 mAh g⁻¹ at 1 C, which decreased to 105.4 mAh g⁻¹ after 100 cycles (corresponding to the retention of 57.8%). The fluorine was also associated to Zr. The capacity retention of Zr and F codoped NCA was raised to 90.5% after 200 cycles at 1 C [86] (see Figure 3 and Figure 4). MgF₂-coated NCA delivers a capacity that is smaller than that of pristine NCA at low C-rate, but the rate capability is better [87].

Improvement of the electrochemical performance at high temperature (60 °C) was also realized by coating the NCA particles with metal oxides. In particular, Cho et al. [88] used SiO₂ and TiO₂ dry coating to stabilize the surface of NCA nanoparticles. The SiO₂ coating involved heating treatment at 700 °C in air, which might induce structural modifications. This difficulty was overcome by Zhou et al. who reported a one-step dry coating of amorphous SiO₂ of an even Ni-richer material: LiNi_0.915Co_0.075Al_0.01O₂. Their 0.2 wt.% SiO₂-coated NCA delivered a capacity of 181.3 mAh g⁻¹ with a capacity retention of 90.7% after 50 cycles at 1 C rate at 25 °C. At 60 °C, the capacity at 1 C was 219.2 mAh g⁻¹ with a capacity retention of 66.8% after 50 cycles, against 54.3% for the pristine sample [89]. The authors then coated the same sample with Zr(OH)₄, which delivered a capacity of 154.3 mAh g⁻¹ after 100 cycles with a capacity retention of 78.1% at 1 C rate at room temperature [90]. Actually, coating materials can be chosen among the high-k gate dielectrics that were extensively studied two decades ago to replace SiO₂ gate in MOSFETs, namely TiO₂, Al₂O₃, Y₂O₃, ZrO₂ (see for instance [91] and citations therein), and indeed, all of them have been considered to coat NCA. For instance, the ZrO₂ coating was effective not only to improve the electrochemical properties, but also in elevating the onset temperature of the dissociation in the charged state This improvement of the thermal stability is due to the suppression of Ni oxidation state changes at the surface [92]. TiO₂ coating was reported by Liu et al. [93], and Al₂O₃ by Du et al. [94]. The 1 wt.% Y₂O₃-decorated NCA exhibited a specific capacity of 181 mAh g⁻¹ after 50 cycles at 0.5 C, against 134 mAh g⁻¹ for the pristine one [95]. Other transition metal oxides have been also considered. When cycled between 2.8 and 4.3 V, the capacity retention of Co₃O₄-coated NCA reached 94.7% after 100 cycles at 0.2 C, and 91.6% at 1 C after 100 cycles [96]. Of course, the homogeneity and thickness of the coat matters and depends on the coating process. In particular, the surface modification by ALD metal-oxide coating (TiO₂, Al₂O₃, etc.) proved to be able to function as a mediator of HF attacks and protection of the NCM cores from corrosion [97]. However, independently of the coating process, the coating improves the electrochemical properties. In addition to the coatings above mentioned, examples include ZnO film deposited by sputtering [98], and coating with Sb-doped SnO₂ nanoparticles via wet-chemical route [99].

Surface modification of LiNi_0.8Co_0.15Al_0.05O₂ nanopowders was also obtained with various other coatings of phosphates, including Ni₃(PO₄)₂ [100]. Li₃PO₄ coating was obtained by exploiting the H₃PO₄, Li₃PO₄, and diammonium hydrogen phosphate as the precursor [101,102,103,104]. LiMnPO₄ was also proposed [105]. However, LiMnPO₄ is insulating, and coating with a more conductive phosphate layer is desirable. More recently, Zhao et al. reported a one-step H₃PO₄ corrosion process to treat the NCA materials in the ethanol solution and obtain a 2 nm-thick amorphous phosphate layer on the primary particles [106]. This electrode delivered a capacity of 153.7 mAh g⁻¹ at 5 C, and 107.5 mAh g⁻¹ after 300 cycles at 5 C, corresponding to a retention of 90%. NCA was also coated with FePO₄ by Huang et al. [107], and more recently by Xia et al. who used a liquid phase process [108]. At 1 C rate, the capacity was 160 mAh g⁻¹, with a capacity retention of 85.82% for the optimized amount 2 wt.% FePO₄. Chen et al. used an industrially viable fusion mixing method to apply Li redox-active LiFePO₄ (LFP) coating. On charging to 4.5 V at 25 °C, the corresponding full pouch cell with graphite anode delivered a capacity of 204 mAh g⁻¹ (per gram of NCA-LFP) and 82.5% capacity retention after 100 cycles. On charging to 4.2 V at 55 °C, NCA-LFP cathodes showed an initial capacity of 201 mAh g⁻¹ and capacity retention of 95% after 150 cycles [109]. The remarkable efficiency of LFP-coating was confirmed by Huang et al. who reported that a NCA modified with 5 wt.% LFP has the best cycling and rate performance, with a higher capacity-retention (89.4% after 200 cycles, at 2 C) [110]. In this work, a simple ball-milling method was used to modify the surface of NCA materials and fill the gaps between particles, a less expensive process than sol–gel, liquid-phase, or ALD coating process, and thus more scalable for industrial development. In a different work, LFP/NCA samples were prepared by adding 20 wt.% LFP with different mass contents to NCA via planetary milling. The discharge capacity and capacity retention ratio were improved by 19% and 17% at 1 C, respectively, with respect to pristine NCA [111]. Pouch shaped full cells that employed TiP₂O₇-coated LiNi_0.80Co_0.15Al_0.05O₂ as cathode were able to perform more than 2200 cycles at 25 °C and more than 1000 cycles at 45 °C before the capacity retention fading to 80% [112]. The initial discharge capacity of the coated sample was 193.1 mAh g⁻¹, against 196.5 mAh g⁻¹. The loss of capacity due to the TiP₂O₇ is thus negligible, while the increase of the cycle ability is remarkable.

The increase of the capacity retention (169 mAh g⁻¹ at current density 360 mA g⁻¹) with respect to that of LiNi_0.80Co_0.15Al_0.05O₂ (350 mA g⁻¹) was reached with a 2 wt.% Li₂O-2B₂O₃ (LBO) glass coating [113]. The cycle life was also improved, with a capacity retention of 94.2% after 100 cycles, while that of the uncoated specimen was 75.3% only. Polysiloxane with ethoxy-functional groups (EPS) was grown on NCA particles through the hydrolysis-condensation method [114]. The corresponding electrode demonstrated a capacity of 159 mAh g⁻¹, with a capacity retention of 96% after 150 cycles under 1 C, to be compared with 85.82 wt.% retention obtained earlier by the FePO₄ coating mentioned above. Srur-Lavi et al. studied the influence of LiAlO₂ coatings obtained by atomic layer deposition (ALD) [115]. Since this process makes possible the control of the thickness of the coat, they determined that the optimum thickness of the coating layer is 2 nm. At C/2.5 rate in the potential range of 2.7–4.3, the retention calculated for cycle numbers 40^th–100^th was raised to 0.15 mAh g⁻¹ per cycle. Moreover, the steady behavior of the electrode cycled with upper voltage cut-off raised at 4.4 and 4.5 V when the delithiation level exceeded 75–80% was improved, while charging above 4.3 V pristine NCA (or NCM) results in structural instability associated to oxygen loss, generation of microstrains, and rapid loss of capacity [116]. These results are in line with those of Rougier et al. who demonstrated an improvement of the electrochemical performance at 40 °C for the LiAlO₂ coated sample [117]. LiAlO₂ coating was also obtained by a simple process (milling NCA with Al(NO₃)₃.9H₂O followed by a heating treatment) [118]. The capacity retention after 100 cycles at 1 C was raised to 94.67%. The discharge capacity at 8 C was 139.8 mAh g⁻¹. Kwak et al. proposed Li₂MoO₄ as the coating material in a sulfide electrolyte. Such an electrolyte is known to be very attractive for all-solid-state cells, but it was not possible so far to use it with oxide cathode materials because of the side reactions. The 1 wt.% Li₂MoO₄ coated electrode with this electrolyte showed a capacity of ≈167 mAh·g⁻¹ at the current density of 8.5 mA·g⁻¹ and 143 mAh·g⁻¹ at 85 mA·g⁻¹. Unfortunately, the cycle ability was tested on 20 cycles only [119]. Li₂TiO₃-coating of NCA improves the capacity retention, especially at high temperature, as the capacity retention after 200 cycles at 60 °C at a rate of 1 C was raised to 91.32% [120]. At room temperature, the uniform 4 nm thick Li₂TiO₃-coating capacity retention to 93.5% after 200 cycles at 0.5 C [121]. LiTiO₂-coated LiNi_0.815Co_0.15Al_0.035O₂ was synthesized through in situ hydrolysis-lithiation [122]. At 1 C, the discharge capacity was 164.1 mAh g⁻¹, and the capacity retention after 100 cycles was 90.8%. The improvement is even more important at high rate: at 10 C, the capacity was still 157.6 mAh g⁻¹. To improve the conductivity, and thus the rate capability, NCA has been coated with graphene nanodots with the size of 5 nm [123]. With 5 wt.% coating, the capacity delivered was raised to 150 mAh g⁻¹ at 5 C. For comparison, three-dimensional NCA/graphene cathode synthesized by template self-assembly exhibited a reversible capacity of 153.6 mAh g⁻¹ with retention of 82.1% after 100 cycles at 5 C discharged rate [124].

The coating materials reported above are lithium-ion conductors, except antimony-doped tin oxide coating [99], and graphene nanodots [122]. Recently, dual-conductive coating consisting of electronically conductive antimony-doped tin oxide and ionically conductive Li₂TiO₃ was applied to NCA. As expected, the rate capability was improved, with a capacity of 153 mAh g⁻¹ delivered at 5 C. In addition, high capacity retention of 88.56% at 1 C-rate and 60 °C after 200 cycles was demonstrated [125].

Electrochemical properties of selected LiNi_0.80Co_0.15Al_0.05O₂ cathode materials are reported in Table 1, illustrating the dependence on the synthesis route, morphology of the particles, and coating, including selected results [126,127,128,129,130,131].

One decade ago, a core-shell structured Li(Ni_0.80Co_0.15Al_0.05)_0.8(Ni_0.5Mn_0.5)_0.2O₂ was experimented [132,133]. The difference between the coating and the core-shell structure lies in the thickness. The thickness of the coating layer is usually few nanometers. The core-shell structure refers to a situation where the thickness of the shell is in the range of submicron to micron order. The results at that time showed an improvement of the rate capability and capacity with respect to pristine NCA, but the cycle life was poor, because the change of volume and lattice distortion during cycling caused the disintegration of the structure. Other works followed in particular with NCM, which will be reviewed in a following section.

3.3.2. Doping NCA

Another strategy used to improve the cycle ability of NCA is the doping. While the coating has little effect on the stability of the bulk material and acts by protecting the surface layer against side reactions with the electrolyte and loss of oxygen during cycling, the doping stabilizes the bulk structure. In particular, K⁺ doping is efficient for this purpose [134], because K⁺ occupies the Li⁺ site and its larger radius prevents the contraction of the lattice associated to the formation of highly resistive NiO at the end of charge, when Ni⁴⁺ can be spontaneously reduced to Ni²⁺ tending to migrate from transition-metal layer to the tri-vacancies in lithium layer [49]. Li_0.99K_0.01Ni_0.8Co_0.15Al_0.05O₂ delivered a capacity of 217 mAh g⁻¹ at 0.1 C. At 1 C, the capacity maintained at 200 mAh g⁻¹, with a capacity retention of 87.4 % after 150 cycles. The Cr doping has two advantages: (i) the redox reactions of Cr³⁺/Cr⁶⁺ can enhance the capacity of NCA [135]; (ii) this doping can promote the activation of Li₂MnO₃ [136]. On another hand, Cu and/or Fe-doping decreases the capacity because Cu and Fe are not electrochemically active in the voltage range 2.8–4.3 V, but this doping improved the cycle ability and rate capability [137].

The capacity retention of Zr-doped NCA after 50 cycles at 0.5 C in the range 2.8–4.3 V was raised to 92%, against 79% for the pristine sample [138]. The 1 mol% Ti-doping of NCA proved to be efficient in maintaining the integrity of the structure and preventing the surface from deterioration even at high voltage. This doped sample delivered a discharge capacity of 179.6 mAh g⁻¹ after 200 cycles at 1 C in the range 3.0–4.5 V, with a capacity retention of 97.4%, in comparison with 167.3 mAh g⁻¹ and 89.2%, respectively, for pristine LiNi_0.80Co_0.15Al_0.05O₂ [139]. Moreover, a very good cycle stability was observed for this doped sample under a cutoff voltage up to 4.7 V, since the capacity remained stable at 170 mAh g⁻¹ between the 30^th and the 100^th cycle at 0.1 C (20 mA g⁻¹) between 3.0 and 4.7 V at room temperature [140]. Surface Te-doping was also efficient to improve the reversibility of the H2↔H3 transition thanks to the suppression of the lattice distortion along the c-axis by strong Te–O bonds, allowing for the use of an upper voltage at 4.5 V. When cycled in the voltage range 2.7–4.5 V at 1 C, the LiNi_0.88Co_0.09Al_0.03O₂ doped with 1 wt.% Te delivered a capacity of 166.9 mAh g⁻¹ capacity after 100 cycles, corresponding to 81.4% retention. At 1 C in the usual voltage range 2.7–4.3 V, the capacity retention was 89.3% after 100 cycles [141].

Since Al doping is intended to increase the structural stability, Liang et al. fabricated a quasi-concentration-gradient LiNi_0.80Co_0.15Al_0.05O₂ cathode material with a high Al concentration that was used as a shell of composition LiNi_0.6Co_0.15Al_0.25O₂ and a core material LiNi_0.80Co_0.15O₂ [142]. Thus modified, this material demonstrated a capacity of 198.1mAh g⁻¹ at 20mA g⁻¹ with 87.8% retention at 0.2 C after 200 cycles; 70.9% at 1 C after 500 cycles. Tian et al. investigated the influence of the surface aluminum concentration on the structure and electrochemical performance of the core-shell NCA material. They demonstrated that Al-doping shrinks the interatomic distance in the transition metal layer but expand the transition metal layers, which facilitates the migration of lithium-ions. They also reported that the Li[(Ni_0.85Co_0.15)_2/3(Ni_0.7Co_0.15Al_0.15)_1/3]O₂ electrode delivered the discharge capacity of 182.6 mAh g⁻¹ with the capacity retention of 91.2% at 0.2 C after 260 cycles [143]. Natarajan et al. exploited the high diffusion of nano-Al(OH)₃ driven by the concentration gradient of Al across the hierarchical hydroxide structure and synthesized LiNi_0.8Co_0.135Al_0.065O₂ with reduced Ni and increased Al at the surface. The capacity retention in the full cell configuration was increased to 91.5% after 150 cycles when cycled between 3 and 4.3 V at 1 C. The capacity loss was reduced to 1% even after 500 cycles by limiting the upper cutoff voltage to 4.2 V [144] (see Figure 5 and Figure 6).

Fe doping improved the cycle ability of NCA owing to the effect of the FeO₆ octahedron on the edge-shared NiO₆ octahedra via enhanced electron localization. In particular, the LiNi_0.80Co_0.075Fe_0.075Al_0.05O₂ material demonstrated a capacity retention of 88.4% at 1 C after 350 cycles [145]. In Na-doped NCA, Na occupies the lithium slab, leading to a small decrease of capacity but large improvement of the cycle ability and rate capability. The Li_0.99Na_0.01Ni_0.8Co_0.15Al_0.05O₂ exhibited a capacity of 184.6 mAh g⁻¹ at 0.1 C, with retention of 90.71% after 200 cycles when cycled at 1 C in the voltage range 2.8–4.3 V [146].

Gui et al. reported a spray-drying doping with liquid polyacrylonitrile (LPAN). After the carbonization of LPAN, the C atoms replace part of O atoms, effectively forming a new compound with cation mixing reduced to 2.7% [147]. As a result, the initial discharge capacity was raised to 227.9 mAhg⁻¹ at 0.1 C, which is 26.6% higher than that of the pristine sample, and the capacity retention rate was found to be 93.59% after 200 cycles.

Mn could be uniformly incorporated into the structure of NCA when the content of Mn is less than 3 wt.% [148]. The size of the primary grains varies from about 800 nm for the pristine NCA, to about 400 nm in the NCA doped with 3 wt.% Mn (called NMCA1 sample). This is an advantage to reduce the microcracks and improve the rate capability, as mentioned in the introduction. At a current density of 0.1 C (1 C = 180 mA g⁻¹) and in a voltage range of 2.8–4.3 V, the NMCA1 delivered initial charge/discharge capacities of 213.3/169.7 mAh g⁻¹ at 0.1 C. At 2 C, the capacity retention over 500 cycles was 89% (from 174.0 to 154.4 mAh g⁻¹), and remained at 81% after 900 cycles. The authors attributed this remarkable result to the infusion of the Mn-containing species into the sphere along crystal boundaries and microvoids at high temperature of the primary grains resulting in the accommodation of the internal strain and few microcracks formed inside the MNCA1 spheres. The electrochemical properties of LCA with various dopants are reported in Table 2.

Surprisingly, only few attempts have been made to improve the Li-rich layer NCA cathode using the synergetic effects of ionic doping combined with surface modification. Mg²⁺ surface doping and Li₃PO₄ coating were simultaneously obtained by mixing the deteriorated NCA with MgHPO₄ precursor, followed by annealing at 750 °C [149]. As a result, the degree of Li/Ni cation-mixing and the amount of surface residual lithium species were reduced. Consequently, the discharge capacities at the first cycle at room temperature at rate 2 C was raised to 168.5 mAh g⁻¹, and was maintained at 142.6 mAhg⁻¹ at the 200th cycles, corresponding to a capacity retention of 84.6%. Simultaneous Mg²⁺ doping and Al₂O₃-coating of NCA were performed to obtain a capacity retention of 99% after 100 cycles and 95% after 250 cycles (from 178 to 168.9 mAh g⁻¹) at 1 C rate [150]. Another advantage linked to the Mg doping is the increased thermal stability, since the thermal runaway temperature of the Mg-NCA battery should exceed that of the undoped NCA battery by 15 °C. This is because the crystal structure stabilization by Mg substitution suppressed oxygen release and reduced the enthalpy in the trigger reaction [151]. A similar synergetic effect was obtained by simultaneous CdO coating and Cd ion doping [152]. The capacity retention in this case was 96.5% and 90.6% after 100 cycles and 200 cycles, respectively, at 1 C. At the higher current rate of 8 C, the initial capacity was 166.2 mAh g⁻¹ and the capacity retention (100 cycles, 3.0–4.3 V) was 95.2%. The Nd₂AlO₃N coating plus Nd³⁺ doping of NCA increased the capacity to 168 mAh g⁻¹ after 200 cycles at 1 C, which amounts to a retention of 91% [153]. This result was attributed to the larger ion radius of Nb³⁺ and stronger Nd-O bond energy that enhanced the kinetics and stabilized the NCA structure. Ti-doping plus Al(OH)₃ coating was also explored, since Ti occupies Li-ions and widens the Li layer spacing and thereby increases the lithium diffusion kinetics, while Al(OH)₃ coating inhibits side reactions. As a result, a capacity retention of 82.2% after 100 cycles at 1 C was demonstrated [154].

3.3.3. Optimization of the Electrolyte

All the results reported we have reported so far were obtained in cells with liquid electrolytes. Attempts were also made in the recent years to fabricate all-solid-state batteries with NCA cathodes. In particular, Liu et al. NCA cathode with a polyvinylidene fluoride (PVDF)/Li_6.75La₃Z_1.75Ta_0.25O₁₂ (LLZTO) composite polymer electrolyte [155]. They found that a gradient cathode with excessive addition of LLZTO on the surface enhanced the cycling performance, due to a localized cation migration region in the surface layer of NCA that suppressed the cation mixing. At 0.5 C (100 mA g⁻¹), a capacity retention of 89% was demonstrated after 50 cycles. A gel-polymer electrolyte (GPE) obtained by in situ polymerization of pentaerythritol tetraacrylate (PETEA) in a liquid electrolyte was used to build NCA/GPE/graphite (NPG) and NCA/GPE/(graphite–Si/C) (NPGS) batteries with energy densities 225 and 228 Wh kg⁻¹, respectively [156]. At 45 °C, the capacities of NPGS and NPG batteries after 280 cycles were 1.88 and 1.99 A h, which corresponds to capacity retentions of 83.9% and 86.4%, respectively. For comparison, those of the same cells with the usual liquid electrolyte instead of the GPE were only 68.9% and 75.7%, respectively. This improvement of the performance shows that the GPE was efficient to form a tight and protective film on the surface of the particles, which the authors attributed to the three-dimensional framework of the GPE.

Another strategy consists in the modification of the surface by an artificial film at the cathode–electrolyte interface (CEI) owing to an appropriate electrolyte. In this spirit lithium difluoro(oxalate)borate (LiDFOB)-based electrolyte was made compatible with NCA by the employment of sulfolane (SL) as a representative sulfur-containing solvent. It actually enhanced the interfacial stability of NCA electrode [157]. The decomposition of LiDFOB on the surface of the positive electrode material contributes to forming a uniform SEI film, which subsequently reduces the dissolution of metal ions and hinders the structure transition of the material from the layered structure to spinel or rock-salt phases. Kim et al. proposed a concept fundamentally different from previously reported cathode modification. They fabricated an artificial CEI by mixing cobalt phosphate composite powder that consisted of Co₂P₂O₇ and Co₃(PO₄)₂ mixed with the NCA before annealing at 700 °C under oxygen atmosphere. During this annealing process, the residual lithium-based impurities on the cathode surface were reduced. The interaction with hydrolysis by-products during the formation of the SEI led to the formation of a homogeneous Li_xPO_y layer and transition metal ion concentration gradient, after rearrangement across the grain boundaries [158]. The LiNi_0.84Co_0.14Al_0.02O₂ cathode with this artificial CEI layer demonstrated a remarkable capacity retention and structural integrity. The tests were performed with the electrode loading level of ≈12 mg cm⁻² and density of ≈3.3 g cm⁻³, which correspond to fabrication conditions for industrial use. At 60 °C, where the operating voltage ranged from 2.8 to 4.4 V (charge and discharge C-rate: 0.5 and 1 C), the capacity maintained at 180 mAh g⁻¹ after 200 cycles. Another process using the grain boundaries was proposed by Yan et al. who demonstrated that infusing the grain boundaries of the NCA secondary particles with a solid electrolyte increases importantly the capacity retention [159]. We will see in the next section different electrolytes and additives that have been tested with NCM811.

4. LiNi_0.8Co_0.1Mn_0.1O₂ (NCM811)

In search of high-power lithium-ion batteries, NCM compounds of various compositions have attracted a lot of attention aiming to enhance both the thermal and the structural stability in order to increase the capacity retention. Actually, the combination of Ni, Mn, and Co can provide many advantages. Figure 7 presents the composition–performance relationship of NCM oxides. As evidenced, the choice of a cathode material is a compromise between the capacity delivered by the cell and its thermal stability. In addition, lithium in excess is usually used during the synthesis, to compensate for the loss of Li that occurs during the sintering process. The lithium in excess in the final sample is in the form of Li₂O, which can easily react with H₂O and CO₂ in the air and consequently convert into LiOH and Li₂CO₃ at room temperature. The residual carbonate would decompose to CO₂ in the formation (charging) process, thus leading to gas expansion and the source of other safety problems [101,160,161]. Among these layered NCM oxides, LiNi_0.8Mn_0.1Co_0.1O₂ has attracted special interest due to its high discharge capacity of ≈200 mAh g⁻¹ at current rate of 0.2 C in the voltage range 2.8–4.3 V. A silicon-graphite//NCM811 18650-type cell from Samsung-SDI exhibits a standard discharge capacity ≥3350 mAh when discharged at 1 C with the voltage limit 2.65–4.2 V. Like in the case of NCA, the upper voltage cutoff of 4.3 V is used to preserve the strong oxidizing property of Ni⁴₊ ions in the delithiated Li_1−xNi_0.8Mn_0.1Co_0.1O₂ phase. At potentials greater than 4.3 V, surface-reconstruction processes giving rise to substantial CO₂ and O₂ release occur, implying that surface-reconstructed layers a few nanometers thick are formed [162]. The situation is thus pretty much the same as in NCA, which is not surprising since the Ni content and the Ni/Co ratio are found to govern the onset, rate, and extent of these surface-reconstruction processes.

4.1. Synthesis

Most of the LiNi_0.8Mn_0.1Co_0.1O₂ are synthesized using the popular coprecipitation technique. Typically, the Ni_0.8Mn_0.1Co_0.1(OH)₂ precursor is prepared by coprecipitation of stoichiometric amount of metal acetate and mixed with LiOH·H₂O at a molar ratio of 1:1.05; then the product is fired at ≈450 and 750 °C in O₂ flow for 5–15 h [163]. Typical electrochemical features of NCMs are displayed in Figure 5 and Figure 6 for powders synthesized by the coprecipitation method and heat treated at 750 °C in oxygen atmosphere. Li et al. [164] investigated the effect of sintering temperature on the electrochemical properties of NCM811 prepared by coprecipitation. The charge–discharge tests showed that NCM powders became better when the temperature increases from 700 to 750 °C, while higher temperature deteriorated the performance. NCM811 with uniform particle size was obtained from Ni_0.8Mn_0.1Co_0.1O₂ precursor prepared by an atomization to form an aerosol via an ultrasonic nebulizer; then the aerosols introduced in a continuously stirring tank reactor (CSTR) were mixed with a NaOH+NH₄OH solution as chelating agent with pH held at 11.5 [165].

Serious capacity degradation of NCM811 materials has been widely reported, i.e., residual lithium compounds (LiOH, Li₂CO₃), chemically unstable Ni-rich surface, antisite defects (cation mixing affecting the layered structure), release of Ni²⁺ ions, phase transformation at high state-of-charge (SOC), cracks arising from the volume change, and surface side reactions. Again, the strategies that have been employed to overcome these disadvantages are doping and surface coating. 4.2. Stabilization of NCM

4.2.1. Coating NCM

Surface modifications of NCM811 are still considered as needed, even though precycling (five cycles at 0.1 C) at high voltage (2.0–4.5 V) and then cycling in lower cutoff voltage of 4.3 V proved to be sufficient to improve the stability of the cathode so efficiently that the capacity retention reached 83% after 500 cycles [166]. As a matter of fact, this forming process is a sort of coating process, as a 3 nm thick cation-mixing nanolayer (≈3 nm) with rock-salt structure is formed on the cathode surface which can efficiently impede further structural degradation. Nevertheless, this monolayer is insulating and coating with a more conductive material is needed to improve the rate capability.

Improved performance was obtained using a coating made of SiO₂ [167], and metal oxides MoO₃ [168], WO₃ [169], LaAlO₃ [170], Al₂O₃ [171,172,173], despite the fact that they are not redox-active. In particular, Al₂O₃ ALD-coated LiNi_0.8Co_0.1Mn_0.1O₂ cathode material delivered a capacity of 212.8 mAh g⁻¹ with coulombic efficiency of 84% at 0.1 C during the first cycle. After 100 cycles, this cathode still demonstrated a capacity of 157.2 mAh g⁻¹, despite the fact that the cycles were performed in the broad voltage range of 2.7–4.6 V vs. Li⁺/Li [171]. Note, however, that this improvement linked to the Al₂O₃ coating is less impressive than in the case of NCA. This can be understood from the work of Han et al. who studied the effect of the composition of NCM on the surface alumina coatings [174]. These authors demonstrated that a good surface protection is achieved with Al₂O₃ coating on NCM532, but this protection effect is hindered when transition metal composition is changed to NCM622 or 811. The reason is the diffusion of surface Al₂O₃ into the bulk when the concentration of Ni is larger than 0.6, transforming the coating layer into a dopant, so that Al₂O₃ in Ni-rich NCM no longer acts as a coating layer, and the surface of NCM811 is no longer protected On another hand, good results were also obtained by coating with an ionic conductor of Li₊ ions [175,176], including Li₂TiO₃ [177], Li₂SiO₃ [178], Li₃VO₄ [179], Li₃PO₄ [180]. These coating layers protect the cathode surface against parasitic redox reaction occurring at the electrode/electrolyte interface. The result is illustrated in Figure 8 and Figure 9 for the case of Li₃PO₄.

Coating can be realized using various methods: atomic layer deposition (ALD), wet process, sonication, in situ reaction. Remarkable results were obtained by atomic layer deposition of LiAlF₄ on LiNi_0.80Mn_0.1Co_0.1O₂ [181]. When cycled at room temperature at 50 mA g⁻¹ current density in the electrochemical voltage range of 2.75–4.50 V vs. Li⁺/Li, the electrode with LiAlF₄ coating demonstrated a capacity higher than 140 mAh g⁻¹ after 300 cycles, which corresponds to 24% decay over 300 cycles. The poor cycle stability at elevated temperatures is a major problem for Ni-rich layered lithium metal oxides [182,183,184]. Testing the capacity retention at 50 °C is thus a real-world relevant test for NCM811. The LiAlF₄-coated material at 50 °C showed an excellent capacity retention with a capacity higher than 150 mAh g⁻¹ after 100 cycles at a higher rate of 200 mA g⁻¹. The epitaxial deposition of Co(OH)₂ nanostructured stabilizer has shown to be efficient to suppress the nickel defects [79]. By a simple dry powder mixing technique, the Co(OH)₂ precursor propagated along the grain boundary and transformed to Co₃O₄ above 300 °C constructing a transition-metal concentration gradient on the surface of NCM811 particles. Improvement of electrochemical performance of NCM811 was also achieved by graphene nanosheets (GrNs) modification [185]. The NCM811-GrN composite prepared by ultrasonication of the pristine material with reduced graphite oxide delivered an initial capacity of 213 mAh g⁻¹ at 0.1 C rate. The role of GrNs is twofold: first is to construct a three-dimensional conductive matrix for NCM8111 particles and second is to suppress the particle aggregation facilitating the electrolyte penetration. After Peng et al. who demonstrated the improvement of Li₃PO₄-AlPO₄ coating [186], Feng et al. proposed a hybrid Li₃PO₄-AlPO₄-Al(PO₃)₃ coating layer to obtain a synergetic effect of a ionic conductor (Li₃PO₄) combined with the thermal stability of AlPO₄. This coat was obtained via reacting Al(PO₃)₃ precursor with the residual lithium (under the form of Li₂CO₃ or/and LiOH) at the surface [187]. The discharge capacity was raised to 201.8 and 218.9 mAh g⁻¹ at 30 and 50 °C at 0.1 C, 85.4% and 78.89% of which were retained after 50 cycles, respectively.

Coating with another phosphate, FePO₄, which was shown to improve the electrochemical properties of NCA [108] was also probed with NCM811. The FePO₄-coated NCM811 powders prepared via a sol–gel method demonstrated a capacity retention of 97% after 100 cycles and 86% after 400 cycles at 0.2 C [188]. Since FePO₄ is a good conductor, the rate capability was also increased, with a capacity maintained at 151.4 mAh g⁻¹ at 5 C. LaPO₄-coated NCM811 demonstrated 91.2% after 100 cycles at 1 C [189], but has not been tested at 5 C. However, since LaPO₄ is an insulator, the rate capability is expected to be reduced, with respect to that of FePO₄-coated NCM811.

B₂O₃-coated LiNi_0.83Co_0.12Mn_0.05O₂ showed superior cyclic stability with a capacity retention of 96.8% and 87.7 % at 1 C after 100 and 200 cycles, respectively, against 69.4 % after 200 cycles for the pristine sample [190]. This result was explained by the fact that B³⁺-doping surface triggers a reduction of a small amount of Ni³⁺ to Ni²⁺, in addition to the fact that it inhibits the irreversible phase transitions and extension of microcracks in the NCM material. It is worth noticing that these results are slightly better than those reported for the Li₂O-B₂O₃ (LBO)-coated LiNi_0.80Co_0.15Al_0.05O₂ tested up to 100 cycles [113]. Since the concentration of Al and Mn are the same, this result suggests that the Mn in NCM has a role similar to that of Al in NCA with the same efficiency to stabilize the structure. The improvement of the electrochemical properties of NCM811 upon LBO coating has been demonstrated not only at room temperature [191], but also at elevated temperature of 60 °C [192].

We have already mentioned the dual coating of NCA to obtain a coating layer that is both an electrical and an ionic conductor [125]. In NCM, a similar approach has been investigated by the use of polymers. Xiong et al. [193] reported the surface modification of NCM811 nanoparticles with conducting polypyrrole (PPy). The nanoscaled PPy coating was realized by facile chemical polymerization method using Fe(III) tosylate as oxidant and ethanol as solvent. Transmission electron microscopy depicted that NCM8111 served as hard template while the PPy layer formed a flocculent and nanofiber coating that effectively alleviated the side reactions between liquid electrolytes and the NCM811 surface. NCM811 was also coated with a dual-conductive layer composed of Li₃PO₄ and polypyrrole (PPy) [194]. On one hand, Li₃PO₄ could improve importantly the ionic conductivity, but also reduce the generation of HF. On the other hand, PPy formed a uniform film which increased the electrical conductivity, made up for the Li₃PO₄ coating defects, and its mechanical properties were efficient to reduce the generation of internal cracks. As a result, the coated-NCM811 delivered a capacity of 159.7 mAh g⁻¹ at 10 C (125.7 mAh g⁻¹ for the bare), with capacity retention of 95.1% at 0.1 C after 50 cycles (86% for the bare). Cao et al. used the conductive polymers that integrate the excellent electronic conductivity of polyaniline (PANI) and the high ionic conductivity of poly(ethylene glycol) (PEG) to coat NMC811 with a homogeneous and thorough PANI–PEG layer [195]. The reversible capacity at 0.2 C at room temperature was 206 mAh g⁻¹, with capacity of 88.4% after 100 cycles. The rate capability was demonstrated by a capacity of 156.7 mAh g⁻¹ at 10 C. At 1 C, the capacity retention at 55 °C was 81.4% after 100 cycles (53.6% for the bare NCM811). Other conductive polymers were considered as materials for coating NCM, such as poly(3,4-ethylenedioxythiophene) (PEDOT) [196,197,198]. However, the polymers do not have any orientation, so that the uniformity of the coating is not warranted and the results not always reproducible. This consideration led Jerng to propose covalent organic frameworks (COFs) as coating materials for NCM, and among them pyrazine (Pyr-2D) contains two nitrogen atoms in its aromatic ring [199]. The advantage of Pyr-2D is not only its planar morphology, but also conjugated bond configuration. Indeed, the Pyr-2D coating improved importantly the electrochemical properties of NCM811 electrodes. In particular, this cathode material was found to be stable in the potential range 2.8–4.5 V, which was thus used to determine the capacity and rate capability. At 600 mA g⁻¹ (1 C), the electrode retained 88.8% capacity after 100 cycles. At 2 C, the capacity was 161.2 mAh g⁻¹. Jiang et al. used polyvinylpyrrolidone (PVP) to assist LiF-LaF₃ multicoating layer on NCM811 by wet coating process. As a cathode, the coated NCM811 delivered a capacity of 173.6 mAh g⁻¹ with the capacity retention of 91.71% after 100 cycles at a high rate of 5 C [200].

Li_1.5Al_0.5Zr_1.5(PO₄)₃ (LAZP)-coated NCM811 cathode was recently fabricated by a sol–gel method [201]. The thickness of the NASICON fast ion-conductor LAZP film was 4 nm. As a cathode, the capacity retention was 78.3% after 300 cycles at 1 C in voltage of 2.8–4.3 V. Moreover, at the higher cutoff voltage of 4.5 V, a sustained reversible capacity of 179.3 mAh g⁻¹ was demonstrated, corresponding to capacity retention of 84.8% after 200 charge/discharge cycles.

SnO₂-coated NCM811 cathode prepared by ball-milling post treatment [202]. For a 3 wt.% SnO₂-coat, the capacity at 0.2 C was 187.5 mAh g⁻¹, with a capacity retention of 90.77% over 50 cycles. Note the results on SnO₂-coated NCA were more impressive with a retention of 91.70% after 200 cycles at 1 C rate at 60 °C [99].

Se-coated NCM811 microspherical cathode materials were prepared via a facile melt-diffusion approach by Ding et al. [203]. Typically, the selenium powder and the NCM811 microspheres were homogenously mixed and then heated at 280 °C for 10 min under the N₂ atmosphere. At this temperature, melt-Se diffuses along the NCM811 microsphere surfaces to achieve the Se-coated NCM811 microspherical cathode materials. This Se-coated NCM811 delivered an initial capacity of 205 mAh g⁻¹ at 0.2 C, 173 mAh g⁻¹ at the 100th cycle at 0.2 C, 132 mAh g⁻¹ at 200th cycle at 2 C, and 103 mAh g⁻¹ at 300th cycle at 5 C. Note the coating process is not only simple, but also efficient. The drawback, however, is that Se is very expensive, which might be prohibitive for practical use at an industrial scale. However, the facile melt-diffusion approach should be promising to coat NCM with other materials.

Recently, however, Chen et al. [204] overcame the problem of surface side reactions between cathode and electrolyte by coating with Li-reactive materials, i.e., Co₃O₄ and LiMn₂O₄ spinel layers, which removed the residual lithium compounds (LiOH, LiCO₃) on the particle surface. During charge and discharge process, the fine surface structure resulted from the generated cubic spinel phase, which suppresses volume change and thus inhibits the formation of surface cracks. Note, however, that Co₃O₄-coated NCM811 did not improve the electrochemical properties with respect to Co₃O₄-coated [96]. In addition, it adds extra Co, while many efforts are presently made to get rid of it. Ryu et al. [205] investigated the storage-induced degradation of NCM811 material and demonstrated an effective way to eliminate the undesirable Li residues via a phosphate treatment, which also suppresses the loss of particle integrity by H₂O and CO₂ infiltration.

Another interesting material design is the full concentration-gradient, which consists in the decrease of Ni content and increase of Co and Mn content across the particle radius (6 µm) [206]. Samples were prepared in a continuously stirring tank reactor containing stoichiometric 811 solution, Ni-poor (111) solution and NH₃·H₂O as the chelating agent. The EDX spectra showed that the outer surface composition was Li(Ni_0.56Co_0.21Mn_0.23)O₂. Not only high discharge capacity, but also good cyclic stability and rate performance were achieved. This cathode delivered a high initial discharge capacity of ≈203 mAh g⁻¹ and a capacity retention of 87.4% after 100 cycles at 55 °C (4.3 V cut-off voltage and 1 C rate). Selected examples of coating technology are listed in Table 3.

The concept of core-shell (CS) consists in the synthesis of particles with Ni-enriched core to maximize the capacity and a Ni-depleted shell to avoid the problems met with the surface layer of the Ni-rich materials. This strategy has been employed for more than a decade, with NCM811 core and LiNi_0.5Mn_0.5 shell [207,208,209,210], and the progress using this strategy was constant through the years [211,212,213,214].

4.2.2. Choice of the Core-Shell Structure

Jun et al. synthesized a CS cathode, consisting of spherical particles with a LiNiO2 core and a 0.5 μm thick NCM811 shell. The average composition was thus Li[Ni0.95 Co0.025Mn0.025]O₂ [215]. In the corresponding full-cell against the graphite anode between 3.0 and 4.2 V at 1 C, the discharge capacity was nearly 190 mAh g⁻¹, retained at 165 mAh g⁻¹ after 1000 cycles, performance that paves the route to the synthesis of lithium-ion batteries with higher energy density. Li et al. fabricated a CS-structured NCM811@0.03[Li−Mn−O] which delivered a capacity of 118 mAh g⁻¹ with almost 82% retention after 200 cycles at the high rate of 10 C, thanks to the stable spinel-structured shell which provided 3D paths for Li⁺ diffusion, while the Ni-rich core insured the high capacity [216]. For the same reason, CS-structured Li[Ni_0.8Co_0.1Mn_0.1)_0.9@ Ni_1/3Co_1/3Mn_1/3)_0.1]O₂ delivered a capacity of 153 mAh g⁻¹ with 90% capacity retention after 100 cycles at 2C rate at 60 °C [217]. These results illustrate the superiority of the CS-structured NMC at high temperature and high rate, provided the shell thickness is smaller than 700 nm [218]. To take full advantage of Ni-rich inner layers and Mn-rich outer layers, a two-sloped full-concentration gradient cathode (denoted as TSFCG) was developed, with a steep gradient in the vicinity of the surface, to reach fast an extended Ni-rich part [219]. The TSFCG-Li[Ni_0.8Co_0.06Mn_0.14]O₂ with the outer surface composition of Li[Ni_0.64Co_0.06Mn_0.30]O₂ demonstrated 94.6% capacity retention after 100 cycles at C/2 rate (105 mAh g⁻¹, 2.7–4.3 V). In addition, Al can be incorporated as a dopant to lower the cation mixing and improve the structural stability. The TSFCG-Li[Ni_0.84Co_0.06Mn_0.09Al_0.01]O₂ [220]. After 100 cycles at 0.5 C, the capacity maintained at 197 mAh g⁻¹ (capacity retention of 95.1%) at 4.3 V and 202 mAh g⁻¹ (capacity retention of 90%) at 4.5 V.

4.2.3. Doping NCM

Another way of stabilizing the structure of NCM is lattice doping with various cations. In the recent years, we can cite doping of NCM 523 with niobium [221] and Nd³⁺ [222]. In the particular case of NCM811 a “top-down” approach has been developed by Weigel et al. for doping with Mg²⁺, Al³⁺, Si⁴⁺, Ti⁴⁺, Zr⁴⁺, Ta⁵⁺ [223]. Attempts to mitigate the volume change and the degradation of the material include doping with calcium [224] and molybdenum [225].

The addition of Zr leads to the coating of NCM811 with a Li₂ZrO₃ [226,227], simultaneously with Zr⁴⁺ doping [228,229,230,231]. In particular, He et al. synthesized NMC811 doped with gradient concentration of Zr⁴⁺ with the Zr-rich Li₂ZrO₃ surface layer [229]. The Li₂ZrO₃ stabilizes the structure and avoids side reactions with the electrolyte, thanks to the strong Zr-O bond. The Zr⁴⁺ dopant has an ionic radius similar to that of Li⁺, so that it occupies partly the Li slabs, reducing the exchange between Ni²⁺ and Li⁺ (cation mixing), even though it increases the amount of Ni²⁺ for charge compensation. Thus modified, this cathode material delivered a capacity of 164.7 mAh g⁻¹ at 10 C and 83.2% capacity retention after 200 cycles at 1 C between 2.8 and 4.5 V. Cr³⁺ plays a similar role, since its ionic radius is also similar to that of Ni²⁺, provided that the Cr-concentration remains small enough to avoid the formation of Cr⁶⁺ on Li-sites [232]. Zhang et al. [233] reported the effect of Ti doping (0.005 mol) on the structural and electrochemical properties of NCM811 prepared by ball-milling technique (particle size of 200–300 nm after 1 h milling). XRD and XPS analyses indicated that the Ti⁴⁺ ions partly substituted the interlayer Li sites and the intralayer Co³⁺ and Mn⁴⁺ positions to retain charge balance in doped NCM material. It showed a high initial specific capacity of 215 mAh g⁻¹ at 0.1 C rate, good rate capability (137 mAh g⁻¹ at 5 C) and cyclic stability (coulombic efficiency of 86.5% after 50 cycles at 5 C). It was stated that Ti doping could decrease the cation disordering and enhance the Li layer spacing with easier Li⁺ ion transport to de-intercalate (charge) and intercalate (discharge). In a comparison between Ti, Mg, and Al-doping, Jiang et al. found that Ti-doping is the most efficient to reduce the cation mixing, and strengthens the most the Ni-O bond, thus reducing gas evolution and increasing thermal and structural stability [234]. The Ti-doped NCM811 electrode exhibited a capacity retention of 93.8% after 200 cycles at 1 C. Sun et al. used a low cost and scalable hydrolysis step to introduce Ti into NCM811 precursor. With a following high-temperature solid-state reaction, Ti diffuses into NCM811 crystals and homogeneously distributed in bulk secondary particles [235]. Ti can effectively enhance ion transfer kinetics and thus greatly improve capacity delivery at high C rates. In addition, the amount of Ni²⁺ in Li sites was decreased from 6.76% to 3.13%, thanks to the charge compensation provided by Ti⁴⁺ to balance electrostatic repulsion. While the upper voltage is usually limited to 4.3 V to avoid the fast decrease of the cycle life due to the H2→H3 transition, Sun et al. performed long cycling tests on the Ti-doped NMC811 in voltage window of 2.8–4.6 V vs. Li⁺/Li at 1 C. Under such conditions, the Ti-doped NMC811 delivered a capacity of 166 mAh g⁻¹ with a capacity retention of 84% over 100 cycles, which is higher than pristine NCM811 (70%, 135 mAh g⁻¹). Na-doping of NCM811 has also been has also been explored, but is not sufficient to prevent the active material from being dissolved in the electrolyte and maintain its structural stability. On another hand, a synergistic modification of sodium ion doping and silica coating was proposed by Zeng et al. [236].

With Zr⁴⁺, Mg²⁺ is the other ion that can occupy the Li sites. Sattar et al. reported that 1 wt% Mg-doped LiNi_0.84Co_0.11Mn_0.05O₂ delivers the discharge capacity of 196.7 mAh g⁻¹ (0.1 C) and maintains the capacity retention of 85.95% after 80 cycles, due to the suppression of the phase transition between H2 and H3 [237].

Considering the success of Al³⁺ doping in NCA, either homogeneous or with Al concentration gradient, including in a material with average composition LiNi_0.815Co_0.15Al_0.035O₂ close to the composition on which we have focused attention in this review [238], many works have explored Al³⁺ in NCM, with formation of homogeneous [239,240,241], concentration-gradient [242,243]. In particular, the improvement of the cycle ability of the Al-doped NCM523 and aging of the cathode in a charged state (4.3 V) at 60 °C results from two effects: (i) the chemical and structural modifications of the solid-electrolyte interface [26], (ii) the stabilization of the structure of NCM via strong Al-O bonding owing to a Al(s)-O(p) overlap [244]. More recently, a 2% molar weight of Al³⁺ doping of LiNi_0.88Co_0.095Mn_0.025O₂ was reported by Yang et al. using an original process [245]. First, laminar primary grains were embedded into the Ni_0.88Co_0.095Mn_0.025(OH)₂ precursor. Then, calcination of the precursor with surface-dispersed nano-Al₂O₃ was made to obtain a homogeneous Al³ doping, with radial arrangement of the primary grains. The LiNi_0.88Co_0.095Mn_0.025O₂-Al_2% demonstrated a capacity retention of 91.57% at 1 C rate after 150 cycles. The rate capability was also enhanced, as the reversible capacities of 172.3 and 165.7 mAh g⁻¹ were delivered at 5 C and 10 C, respectively. A comparison between the electrochemical properties of Li[Ni_0.89Co_0.05Mn_0.05Al_0.01]O₂ (NCMA), NCM, and NCA with similar Ni contents demonstrated the superior behavior of NCMA [246] (see Figure 10). The NCMA delivered a capacity of 228 mAh g⁻¹ at 0.1 C (18 mA g⁻¹) at 30 °C. The full cell with a graphite anode demonstrated a capacity retention of 84.5% after 1000 cycles at 1 C. The NCMA even with a small Al concentration of 1 mol.% outperformed the NCA and NCM cathodes both in terms of capacity and cycle ability (see Figure 11). The authors also demonstrated that the reason for this remarkable result is due to the fact that the Al-doping prevents the large anisotropic variation of the lattice parameter in the c-direction at the H2→H3 phase transition. This reduced strain for the NCMA cathode results in reduced or lack of microcracks in the secondary particles, at contrast with NCA and NCM. Moreover, the differential scanning calorimetry (DSC) analysis demonstrated an increase of the thermal stability in NCMA, with its exothermic peak temperature at 205 °C and heat generation of 1384 J g⁻¹ (see Figure 12). On another hand, the temperature inducing change to the rock-salt structure accompanies with oxygen loss and is as low as 250 °C for aged NCA, causing severe safety problems [247].

Liang et al. performed a DFT calculation to study the doping effects of Mg²⁺, Al³⁺, Ti⁴⁺, Zr⁴⁺, Si⁴⁺, Ga³⁺, and V⁵⁺ and their impact on structural and electrochemical properties (see Figure 13) [248]. As a result, the co-substitution of Ti or Zr at Co sites and Al at Mn sites has been proposed as a promising multidoping strategy. DFT calculations also suggested codoping with Al and Mg dopants, in which case Al and Mg occupy preferentially the Ni and Li sites, respectively [249]. On another hand, P- and F-codoping of NCM811 was considered by Yuan et al. The corresponding material demonstrated a capacity retention of 94.4% (162.3 mAh g⁻¹) after 100 cycles at 0.5 C [250].

Liu et al. combined Cr ionic doping together with surface coating with the fast ion conductor LiAlO₂, but only on a Ni-poor 3 wt.% LiAlO₂-coated Li_1.2Ni_0.16Mn_0.56Cr_0.08O₂ [251]. Moreover, the good results obtained on NCM with such a small Ni concentration might not extend to the case of NCM, taking into account the higher diffusion of Al in Ni-rich NCM [174]. On another, hand, Xin et al. obtained a Li–Nb–O coated and substituted NCM811 by wet chemistry in a single step treatment [252]. Owing to the synergetic effects of the protective surface coating and doping by Nb⁵⁺ incorporation into the bulk structure, the rate capability was improved, with a capacity of 158 mAh g⁻¹ delivered at 2 C) as well as the capacity retention (89.6% vs. 81.6% after 60 cycles). However, without any coating, Li et al. reported that NCM811 cathode simply doped with 1 at.% Nb prepared through a two-step sol–gel method demonstrated a capacity retention of 94.55% after 100 cycles at 1 C, and a good rate capability with a capacity of 151.46 mAh g⁻¹ at 5 C [253].

A similar approach consisted in the synthesis of NCM with a gradient-concentration of La³⁺ and Y³⁺ rare earth cations. In the first case, a cation-mixed (perovskite phase) layer of La₂Li_0.5Co_0.5O₄ was formed at the surface of NCM811, with gradient concentration La³⁺ inside the particles. As a cathode, it delivered 95.2% of its initial capacity after 100 cycles at 1 C [254]. In the case if yttrium, a Y₂O₃ surface layer was formed with gradient concentration Y³⁺ inside the particles. The 2 mol% Y-modified sample demonstrated a capacity retention of 98.4% after 100 cycles (0.5 C rate, 2.8–4.5 V) [255]. Wu et al. modified the surface of NCM811 with the perovskite-like La₂Ni_0.5Li_0.5O₄ [256]. In addition, during the high-temperature synthesis process, La³⁺ ions are also doped into the subsurface lattice of NCM811, so the final product combined synergetic effects of doping and coating. As a result, when cycled in the range 2.75–4.5 V, the first discharge capacity at 0.2 C of the La-modified sample is 229.3 mAh g⁻¹ and the 200th capacity retention ratio at 1 C has been improved from 63.7% to 90.1%. The electronic properties of selected doped-NCM materials are reported in Table 4.

4.2.4. Optimization of the Electrolyte

Unstable cathode–electrolyte interface (CEI) degrades the electrochemical properties of NCM cathodes at high voltages. The different mechanisms responsible for this instability (surface phase transitions, cracking, Ni dissolution, electrolyte decomposition, oxygen release) have been reviewed elsewhere [257]. The formation of the (CEI) could enter in the section devoted to the coating. However, the approach which consists in optimizing the CEI via the appropriate choice of the electrolyte is different. In addition, the recent progress obtained by the choice of electrolyte to optimize the CEI justifies a separate section. Conventional flammable organic liquid electrolytes that are used in all the works reported in this review are typically composed of 1 mol L⁻¹ LiPF₆ salt in ethylene carbonate (EC) and linear carbonate(s), for instance ethyl methyl carbonate (EMC). Different additives have been considered to adapt the electrolyte to the high operating voltage of NMC811 and minimize undesired reaction at the interface. The efforts to control the CEI of NCM811 have been reviewed in [258] and we refer to this former review for additives prior to 2019.

Different attempts have been made to find electrolyte additives that would stabilize the surface of NCM materials. They have been reviewed in [259]. More recently, a functional vinyl -C=C- group allylboronic acid pinacol ester (ABAPE) was introduced as a film forming additive [260]. The LiNi_0.8Co_0.1Mn_0.1O_2/graphite pouch cells which contained 1.5% ABAPE demonstrated 87.7% capacity retention compared with 71.8% of blank electrolyte after 500 cycles. This improvement is due to the oxidization of ABAPE prior to blank electrolyte on the cathode, which prevents the electrolyte decomposition, and results in the formation of a protective surface layer. 4, 5-difluoro-1, 3-dioxolan-2-one (DFEC) was reported as a film forming additive to enhance the electrochemical performance of LiNi_0.8Co_0.1Mn_0.1O₂//SiO@C full cells [261]. The cells with 2% DFEC keep the best capacity retention of 88.7% after 500 cycles comparing to 83.9% of blank group. Note, however, that this additive had no significant effect on NCA, the improvement being attributed to the formation of the film on the anode side, not on the cathode. Thioether-substituted diaminocyclopropenium redox-reactive cation was proposed as an electrolyte additive by Ji et al. [262]. This organic cation demonstrated an electrochemical reversibility at ≈4.55 V vs. Li⁺/Li and solubility (0.5 M) in carbonate-based electrolyte. With 0.2 M addition, the LiNi_0.8Co_0.1Mn_0.1O_2//graphite cell survived 54 cycles at 0.2 C with 100% overcharge. It also supported an utmost 4.4 mA cm⁻² (2 C) with 100% overcharge and delivered a maximum capacity of 7540% SOC at 0.2 C. Peng et al. developed a highly concentrated acetonitrile (AN)-based electrolyte with a vinylene carbonate (VC) additive. The VC leads to the formation of a polycarbonate-based SEI that minimizes Li corrosion, which results in a very high Li CE of 99.2% at 0.2 mA cm⁻² [263]. Stable cycling of Li|AN-electrolyte + VC|NCM622 cells with a high cathode loading of 4 mAh cm⁻² was demonstrated, but it was not tested with NCM811, yet. Among the new performing additives, we can mention 4,5-Dicyano-1,3-dithiol-2-one (DDO), as 0.1 wt.% DDO in the electrolyte raised the capacity retention of NCM811 to 75.59% after 200 cycles, against 15.11% only for the blank electrolyte [264]. Kong et al. chose sulfolane to be oxidized in advance and built a protective film around NCM811. Moreover, they employed fluoroethylene carbonate to be reduced prior and form a film on the face of silicon oxide-graphite negative electrode. The full NCM811//SiO_x-graphite anode with this modified electrolyte demonstrated a capacity retention of 77.51% after 200 cycles with upper voltage at 4.5 V [265]. With 0.5 wt.% N,O-bis(trimethylsilyl)acetamide (BSA) additive, NCM811 demonstrated improved capacity retention of 86% after 200 cycles at 1 C, while it shows only 69.4% with the baseline electrolyte [266]. Another film-forming electrolyte additive is 2,4,6-triphenyl boroxine (TPBX), which increased the capacity of NCM811 from 57% to 78% after 200 cycles at 1 C in a half-cell [267]. The performance of the graphite//NCM811 full cell was also improved importantly with this additive in the electrolyte, because the TPBX is also reduced earlier than the ethylene carbonate and forms on the graphite anode a conductive SEI. A similar benefit for both the NCM cathode and graphite anode was demonstrated with phenyl trans-styryl sulfone additive [268]. Tris(trimethylsilyl) phosphite (TMSPi) was introduced as an electrolyte additive and improved the electrochemical performance of the NMC811/Si–Gr full cells through formation of protective surface layers at the electrode/electrolyte interfaces [269]. However, the cycle ability has been tested on 50 cycles only.

Remarkable results were reported with LiNi_0.76Mn_0.14Co_0.10O₂, an NCM with composition close to that of NCM811, owing to an optimized electrolyte (0.6 mol L⁻¹ lithium bis(trifluoromethanesulfonyl)imide + 0.4 mol L⁻¹ lithium bis(oxalato)borate + 0.05 mol L⁻¹ LiPF₆ dissolved in ethylene carbonate and ethyl methyl carbonate (4:6 by weight)) [270]. Excellent stability at a high charge cutoff voltage of 4.5 V was demonstrated in a cell with lithium metal anode, with a discharge capacity larger than 220 mAh g⁻¹ (846 Wh kg⁻¹) and capacity retention higher than 80% capacity after 1000 cycles at 2 C rate.

A new class of nonflammable organic liquid electrolyte has been recently proposed, consisting in 1 mol L⁻¹ LiPF₆ in propylene carbonate (PC) and fluorinated linear carbonate(s) [271]. The substitution of a flammable electrolyte by a nonflammable electrolyte has the first obvious advantage to improve importantly the safety of the battery, especially as the Li-ion batteries on Ni-rich cathodes are subject to battery fires [64]. However, these new electrolytes also proved to improve importantly the performance of these cathodes. The pristine NCM811 combined with the electrolyte composed of 1 mol L⁻¹ LiPF₆/PC/methyl(2,2,2-trifluoroethyl) carbonate (FEMC)/di-(2,2,2 trifluoroethyl)carbonate (DFDEC) demonstrated remarkable electrochemical properties [272]. Under the high charge cutoff voltage of 4.5 V, the NCM811 in a half cell with this electrolyte demonstrated a capacity of 230 mAh g⁻¹ with retention of 95% after 100 cycles at 0.2 C. Due to the interfacial incompatibility between PC and graphite, this electrolyte cannot be used with a full cell equipped of a graphite anode. In this case, 1 wt.% vinylene carbonate (VC) was added to the electrolyte, as a SEI-forming electrolyte additive for graphite anode, which did not change the nonflammable properties [273]. With this SEI-forming additive, the NCM 811 in graphite//NCM811 full cells delivered 250 mAh g⁻¹ at 0.2 C with 82% retention after 50 cycles. In this work, the authors also visually proved reduced crack formation and metal-dissolution via electron microscopy analysis. Therefore, even though initial formation of cracks comes from structural stress [66,159,274,275], their development with cycling can be significantly reduced and controlled with the use of a functional electrolyte that stabilizes the CEI. Note the choice of the VC additive chosen by Pham et al. may not be the best choice, since Qiu et al. demonstrated that diphenyl or methylphenyl carbonate outperforms vinylene carbonate as additives of electrolyte in NMC811//graphite cells [276]. Li et al. reported that the cycle life of LiNi_0.94Co_0.06O₂ is greatly extended when lithium bis(oxalate) (LiBOB) is added in the electrolyte [277], but no test with NMC811 has been made, yet. On another hand, the addition of only 0.5 wt.% triphenylphosphine oxide (TPPO) into a standard electrolyte (LiPF₆ in EC:EMC 3:7 by weight) increased the first cycle Coulombic efficiency and the reversible specific capacity; it also improved the capacity retention of the NMC811//graphite cell cycled between 2.8 and 4.3 V [278]. After 100 cycles at 0.5 C, the capacity was still 172 mAh g⁻¹, corresponding to a capacity retention of 92%. Jo et al. determined that monobasic sodium phosphate (NaH₂PO₄) (P2) additive improves the thermal stability of NCM811 not only by the formation of a conductive CEI, but also because it decelerates the formation of NiO-phase on the cathode by controlling the hydrofluoric acid content [279].

An NMC811-based all-solid-state lithium battery (ASSLB) using sulfide electrolyte was fabricated by Li et al. [280]. The NMC811 was first coated with LiCoO₂ to form core-shell NCM-LCO via coprecipitation method. Then, NCM@LCO material with Ni-poor surface was obtained via high temperature solid phase method. Finally, the NCM@LCO particles were coated with LiNbO₃ via a wet coating method to obtain the cathode material, which demonstrated a capacity retention of 80% after 585 cycles at 0.612 mA cm⁻². Recently, Cui et al. [281] selected methyl diphenylphosphonate (MDPO) as additive, which widened the electrochemical window up to 5.0 V and stabilized the coulombic efficiency of the NCM811 cathode. Furthermore, MDPO plays an important role for the thermal stability of the cell.

Mao et al. proposed to replace LiPF₆ by lithium difluoro(oxalato)borate (LiDFOB) salt [282]. Owing to the decomposition reaction of LiDFOB, the in-situ hierarchical CEI presents a two-layered structure, where the inner layer is rich in LiF and outer layer mainly contains organic components such as Li_xBO_yF_z. With the LiDFOB based electrolyte, The NCM811//Li cell delivered a capacity of 127.5 mAh g⁻¹ at 10 C, with capacity retention of 69.8% after 400 cycles (17.1% with the LiPF₆-based electrolyte).

4.2.5. Aqueous Processing

Aqueous electrode processing has advantages. Manufacturing costs are lower compared to traditional processing using N-methylpyrrolidone (NMP). In addition, overexposure to NMP is dangerous for health. Therefore, aqueous process also offers environmental benefits [283,284,285]. Water soluble binders also facilitate LIB recycling. For these reasons, water-based processing is widely used for graphite anodes. On another hand, it is difficult to adopt this process for cathodes, due to adverse effects of water on NCM materials of different compositions [286,287,288,289]. In particular, transition metal oxides produce basic solutions in water [290,291,292,293]. In particular, the exposure of NCM811 to humidity results in the formation of surface impurities and decomposition of the surface layers and these effects are correlated with nickel content [294,295,296]. On the other hand, Xiong et al. reported that NCM811 water exposure reduces the capacity, but decreased the capacity fade, and increased the structural stability [297]. Recently, Wood et al. reported a systematic investigation of the water stability of four different NCM cathode powders with varying nickel contents, including NCM811 [298]. Pouch cells made with aqueous-processed NMC 811 cathodes showed 70% capacity retention through 1000 cycles at C/3 rate. The carboxymethylcellulose/acrylic emulsion binder used instead of the standard polyvinylidene difluoride (PVDF) binder resulted in a lower rate capability above 1 C current rate. NMC 811 only showed 3 wt.% Li⁺ dissolution under typical processing conditions, and yet the observed Li⁺ leaching did not correspond to a lower initial capacity. This work then opens the route to implementation of aqueous processing of Ni-rich NMC in future battery production lines, which will enable higher cell energy densities at lower cost.

5. The Route to Co-Free Ni-Rich Batteries

We have reported the state-of-the-art of Ni-rich NCA, NCM with the Ni composition x = 0.8, which is the highest concentration commercialized today. It does not mean that the fabrication of Li-ion batteries with larger Ni concentrations is hopeless. As reported in this review, full-gradient and core-shell structured cathode particles opened the route to average compositions with a x-concentration larger than 0.8. Attempts have even be made to use this technique to synthesize Co-free electrodes. A Co-free precursor with a 16 μm Ni(OH)₂ core and 1 μm Ni_0.8Mn_0.2(OH)₂ shell was reacted with LiOH.H₂O at 750 °C to obtain retain a well-defined core–shell structured material. As a cathode, it exhibited higher specific capacity than NMC811, while the cycling performance was equivalent to NMC811 [299]. A cost-effective cobalt-free LiNi_0.9Mn_0.1O₂ was also synthesized by using a coprecipitation method; as a cathode, it delivered capacity of 190 mAhg⁻¹ in the first cycle at a rate of 0.2 C, and a capacity retention of 93 % over 150 cycles at 2.7–4.3 V [300]. Particles with a Li[Ni_0.94Co_0.038Mn_0.022]O₂ core and a 1.5 µm thick concentration gradient (CG) shell with the outermost surface composition Li[Ni_0.841Co_0.077Mn_0.082]O₂ was fabricated by differential coprecipitation process [301]. The average composition was then Li[Ni_0.9Co_0.05Mn_0.05]O_2,, reducing the Co content to a residual concentration. The radial texturing of the shell layer, which is specific to the core-shell and gradient concentration process, protracts the detrimental H2→H3 phase transition responsible for the microcracking. As a consequence, this compositionally partitioned Li[Ni_0.9Co_0.05Mn_0.05]O₂ cathode delivered a capacity of 229 mAh g⁻¹ and exhibited 88% capacity retention after 1000 cycles in a full cell. The concepts of core-shell, concentration gradient two-sloped full-concentration gradient cathodes are then very promising to increase the electrochemical performance of LIBs based on Ni-rich cathodes. Moreover, the process used to synthesize CS and CG precursors for subsequent target production is coprecipitation because of the unique growth mechanism of spherical particles. Actually, the coprecipitation reaction proved to be very efficient to fabricate spherical high-tap density precursors at the industrial level [302]. These authors argued that it is greatly tough to manufacture in multiple identical copies CG cathodes for large-scale usage. On another hand, the fabrication of the CS structure is much easier. The main difficulty is the high cost due to the batch-wise system. Nevertheless, all these problems found a solution, since the South Korean cathode manufacturer EcoPro BM commercialized already NMC811 with the concentration-gradient process, and SK Innovation (trade mark) will develop this year with EcoPro BM such an NMC811-based cathode to which will be added a separator to improve the stability [303]. Still, however, high-capacity Co-free electrodes with a cycling life the order of 1000 cycles required for industrial development is still to be demonstrated, but hopefully, it should be demonstrated within few years.

The various coatings, doping strategies, electrolyte enhancement that we have reviewed did improve the electrochemical performance. The difficulty is to find one of them that can solve all the problems simultaneously. For instance, conductive coating improves the safety and rate capability by facilitating the Li⁺ diffusivity, but often fails to improve the mechanical problems responsible for the microcracking of the particles. One solution has been found with TiP₂O₇-coated NCA as a cathode in a full cell was able to perform more than 2200 cycles at 25 °C and more than 1000 cycles at 45 °C before the capacity retention fading to 80% [111]. Doping improves the structural stability of the material. The best result was obtained with Al-doping, which was able to suppress the microcrack nucleation and propagation in Li[Ni_0.89Co_0.05Mn_0.05Al_0.01]O₂. In a full cell with graphite anode it was able to deliver a high capacity with 84.5% after 1000 cycles at 1 C [246]. Even at 45 °C, the cycle life was 500 cycles. This material is a hybrid of NCA and NCM. It is very difficult to increase the cycle life up to 1000 cycles with NCM811 alone. It can be used, however, in a core-shell structure of spherical particles designed to a LiNiO2 core and a 0.5 μm-thick NCM811 encapsulating shell, which fulfilled this goal [214]. As recalled above, the radial texturing was essential to achieve the outstanding performance of the compositionally partitioned Li[Ni_0.9Co_0.05Mn_0.05]O₂ material. This is the motivation to synthesize a new class of Ni-rich NMC and NCA with a modified microstructure similar to the texture met in gradient concentration and core-shell processes. This can be achieved by doping with boron [304]. Boron-doped at the level of 1 mol% Li[Ni_0.9Co_0.05Mn_0.05]O₂ obtained by the addition of B₂O₃ during the lithiation of the hydroxide precursor has a highly textured microstructure similar to that of gradient cathodes [304]. This cathode delivered a capacity of 237 mAh g⁻¹ at 4.3 V, and demonstrated a remarkable capacity retention of 91% after 100 cycles at 55 °C. The performance is still outperformed by the compositionally partitioned material with the same average composition, but is much better than the un-doped Li[Ni_0.9Co_0.05Mn_0.05]O₂. Microstructure modified cathodes were obtained by doping with aluminum [245,305]. The capacity retention of the homogeneous 2% molar weight Al³⁺ doped LiNi_0.88Co_0.095Mn_0.025O₂ was raised to 91.57% at 1 C rate after 150 cycle, owing to the radial arrangement of primary grains. The last example is tungsten-doping [306], also differing from the usual coating in that the primary crystallites keeps the coherency of the secondary particle. In this work, Ryu et al. substituted W for Al in NCA to produce Li[Ni_0.9Co_0.09W_0.01]O₂ (NCW90), which had two benefits: (i) the presence of microfractures absorbing the strain field caused by the H2→H3 phase transition; (ii) reduced primary particle size, which restricts the concentration of grain boundaries where microcracks nucleate, and facilitates the accommodation of the volume change during cycling. As a consequence, this cathode delivered a capacity of 231.2 mAh g⁻¹ at 0.1 C, with capacity retention of 92% after 1000 cycles.

6. Conclusions

NCA, NCM, NCMA cathode materials with Ni concentrations of 80% already reach the commercial step. We have reviewed the efforts in research, and solutions that have been found to reduce the concentration of antisite defects, to mitigate the side reactions (Ni⁴⁺ oxidizing electrolyte, Co dissolution) and surface reconstructions, and to extend the voltage range up to 4.5V. The knowledge acquired in the optimization of these materials opens the route to the rapid industrial development of even Ni-richer compounds with reduced concentration of cobalt. We have already warned repeatedly the need to decrease as much as possible the concentration of cobalt in the batteries, not only because Co is toxic and expensive, but also because the conditions of extraction are repeatedly denounced by Amnesty International and the International NGOs [64]. The decrease of Co concentration and ultimately Co-free cathodes with these lamellar compounds will not necessarily reduce the cost of the batteries, because the cost of fabrication of the particles with the appropriate structure and the control of the synthesis parameters will be high, but the electrochemical performance in energy density will be greatly improved, and will respond to the demand for specific applications such as electric cars when extended driving range is needed.

The weakness of the high-Ni batteries remains their poor thermal stability and severe thermal runaway [307], even though the modifications we have reviewed in the present work improve the situation. The security of these batteries will thus rely still for years to come on a sophisticated battery monitoring system (BMS). We have also pointed out how important it is to investigate the stability of the cells at elevated temperature at 50–60 °C, needed for practical use. Elevated temperature usually improves the capacity and rate capability, but affects the cycle ability. Now that the state-of-the-art in these materials reach the performance needed for commercial use, the report of the electrochemical properties should be more systematic in on-going publications. Attention should also be paid to the pellet density. In most cases, the electrochemical properties of the Ni-rich cathodes have been reported in the case of the low electrode density (≤3.4 g cm⁻³) and loading level (<8 mg cm⁻²), although recent works report active material loading mass of ≈11 mg cm⁻² [308]. Moreover, as the nickel concentration increased, the commercially available electrode density decreased because of the collapse of the secondary particle during electrode pressing process. Kim et al. pointed out that this could give rise to a large gap between academic research and practical application of the nickel-rich cathode materials [309]. They concluded that the collaborative efforts between the academics and the industrial fields should be expanded.

The present review also reveals that most of the publications reporting advances in the fabrication of performing Ni-rich-based batteries only consider one aspect: either a modification of the cathode particles or the effect of an additive in the electrolyte; a minority of the publications investigate the synergetic effect of multidoping, or doping plus surface modification, and rarely the synergetic effect of modification of the particles and the optimized electrolytes. At this stage, it should then be very useful to investigate such synergetic effects if only to verify their compatibility. Additionally, most of the full cells that have been investigated use the standard graphite anode, while there are now more performing anodes mixing graphite and SiO_x [310]. More collaborations between research teams over the world need to be forged to compare knowledge and add skills related to these different elements of the batteries, considering the urgency to find sustainable ways to store the 10¹² kWh/yr that is needed for mankind.

Figure 1. Specific capacity (mAh g-1) versus capacity retention over 100 cycles (%) plot of various layered NCM and NCA cathodes showing the trade-off between stability and capacity at increasing Ni content. Compounds are labelled by their composition (Ni, Co, Mn) = x:y:z. Reproduced from [16]. Copyright 2017. The American Chemical Society.

Figure 2.(a) Layered structure of NCM compound. Colors of atoms are green (Li), red (O), and silver/purple/blue are Ni, Mn, Co transition-metal cations, respectively. (b) Tetrahedral site pathway. (c) Oxygen dumbbell pathway for Li+ ions.

Figure 3. Synthesis schematic diagram of Li(Ni0.80Co0.15Al0.05)1-xZrxO2-yFy. Reproduced with permission from [86]. Copyright 2019 Elsevier.

Figure 4. Electrochemical properties of Li(Ni0.80Co0.15Al0.05)1-xZrxO2-yFy (x = 0, y = 0.01, labeled F-1; x = 0.01, y = 0, labeled Zr-1; x = 0.01, y = 0.01, labeled Zr-F-1; x = 0.02, y = 0.02, labeled Zr-F-2). (a) Initial charge-discharge curves for all samples at 0.2 C; (b) rate performance at various rates and (c) cycling performance at 1 C. Reproduced with permission from [86]. Copyright 2019 Elsevier.

Figure 5. Schematic representation of various stages in the formation of LiNi0.8Co0.135Al0.065O2 particles CC-O (compositionally constant) and CG-O (compositionally constant core with the graded surface) during the precipitation and high-temperature calcination. Reproduced with permission from [144]. Copyright 2020 American Chemical Society.

Figure 6.(a) Charge-discharge plateau of formation cycle, at 0.1 C rate and 1 C in full cells with CG-O cathode (see Figure 5) and graphite anode in the voltage range of 3.0-4.3V. (b) Normalized full cell cyclic stability 1 C rate in the voltage range of 3.0-4.3V of CC-O and CG-O. (c) Cyclic stability of CG-O in the voltage range of 3.0-4.2V. (d) Comparison of cyclic stability of CG-O with different electrolytes. Reproduced with permission from [144]. Copyright 2020 American Chemical Society.

Figure 7. The composition-performance relationship of layered nickel-manganese-cobalt oxides (NCM). The choice of a cathode material is a compromise between the capacity delivered by the cell and its thermal stability.

Figure 8. Schematic illustration for the fabrication of the NCM811@Li3PO4. Reproduced with permission from [180]. Copyright 2020 Elsevier.

Figure 9.(a) Schematic illustration for the fabrication of the pouch-type full Li-ion cell with NCM811@Li3PO4 cathode and C-Si anode. Electrochemical properties of the full cell: (b) voltage-capacity curves and (c) differential capacity curves. (d) The initial charge-discharge plots (0.1 C) and (e) long-term cycling stability (1.0 C). Reproduced with permission from [180]. Copyright 2020 Elsevier.

Figure 10. Spider chart of electrochemical performance of Li[Ni0.89Co0.05Mn0.05Al0.01]O2 (NCMA89). Reproduced with permission from [246]. Copyright 2019 The American Chemical Society.

Figure 11. Comparison of electrochemical performance of the NCA89, NCM90, and NCMA89 cathodes in half-cells with Li metal anode. (a) First cycle voltage profiles for the three cathodes at 0.1 C at 30 °C. Cycle ability of the three cathodes were tested in voltage ranges of (b) 2.7-4.3 and (c) 2.7-4.5 V at 0.5 C and 30 °C. Long-term cycling performance of the NCA89, NCM90, and Li[Ni0.89Co0.05Mn0.05Al0.01]O2 (NCMA89) cathodes using pouch full cells at 1 C and (d) 25 and (e) 45 °C with a voltage range of 3.0-4.2 V with mesocarbon microbead graphite as an anode. Reproduced with permission from [246]. Copyright 2019 The American Chemical Society.

Figure 12. DSC profiles for the NCA89 (i.e., NCA with 0.89 Ni), NCM90, and Li[Ni0.89Co0.05Mn0.05Al0.01]O2 (NCMA89) cathodes measured in their second charged state (Li0.3MO2) in the presence of 1.2 mol L-1 LiPF6 EC:EMC = 3:7 by vol.% with 2 wt.% VC. Reproduced with permission from [246]. Copyright 2019 The American Chemical Society.

Figure 13. Spider plots of doping impact of each element (at Co and Mn sites) on different electrochemical and structural properties of NCM811. Reproduced with permission from [248]. Copyright 2017 Royal Society of Chemistry.

Synthesis Method	Characteristics	Electrochemical Performance	Ref.
Solid-state reaction sintered at 720 °C for 28 h	Microspheres	180 mAh g−1 at 0.2 C; CR of 87% after 76 cycles at 1 C	[126]
Two-step coprecipitation sintering in O2	Microrods, SSA of 0.5 m2 g−1	218 mAh g−1 at 0.1 C; CR of 93% after 100 cycles at 1 C in range 2.7–4.3 V	[127]
Coprecipitation with 5-sulfosalicylic acid as chelating agent	Secondary spherical particle 8 µm dia.	203 mAh g−1 at 0.1 C; CR of 93.3% after 200 cycles at 1 C in range 3.0–4.3 V	[128]
Coprecipitation heated at 750 °C under O2 stream	0.5–1.5 µm particle size agglomerates of 20 µm 0.23% cation mixing	177 mAh g−1 at 0.1 C; CR of 82% after 500 cycles at 2 C rate in range 3.0–4.1 V	[129]
Coprecipitation sintered at 750 °C	400–600 nm particle size polyhedral shape	200 mAh g−1 at 0.2 C; 92% CR after 60 cycles at 1 C	[130]
Ball milling with LATP Sintered at 750 °C in O2	10 µm spherical particle 200 nm thick coating	180 mAh g−1 at 0.1 C; CR of 88% after 100 cycles at 2 C rate in range 2.8–4.3 V	[131]
Coprecipitation, sintered at various O2 pressures optimized for 0.1 MPa	Sphere-like 15 µm dia.	166 mAh g−1 at 0.1 C; CR of 87% after 100 cycles at 1 C rate in range 2.8–4.3 V	[25]
Polysiloxane coating Hydrolysis condensation	Spherical agglomerates 20 µm dia.	184 mAh g−1 at 0.1 C; CR of 96% after 150 cycles at 1 C rate in range 2.8–4.3 V	[114]
Li2O-2B2O3 coating by a solution method	Commercial LCA	169 mA g−1 at 360 mA g−1; CR of 94.2% after 100 cycles in the range 3.0–4.3 V	[113]
LiAlO2 coating by ALD	Commercial LCA	198 mAh g−1 at C/5 in the range 2.7–4.5 V; CR 91% between 40th and 100th cycle	[115]
LiAlO2 coating by milling	Spherical agglomerates 20 µm dia.	172.3 mAh g−1 at 1 C; CR of 94.67% after 100 cycles at 1 C in the range 3.0–4.3 V	[118]
Li2TiO3 coating by near-equilibrium deposition	Spherical agglomerates 6–8 μm dia.	187.5mAh g−1 at 0.5 C; CR of 93.5% after 200 cycles at 0.5 C in the range 2.8–4.3 V	[121]
LiTiO2 coating by hydrolysis	Spherical agglomerates 3–15 μm dia.	164.1 mAh g−1 at 1 C; CR of 90.8% after 100 cycles at 1 C in the range 2.8–4.3 V	[122]
Dual coating Sb-doped SnO2 and Li2TiO3	Spherical agglomerates 10 µm dia.	153 mAh g−1 at 5 C; CR of 88.56% after 200 cycles at 1 C at 60 °C in the range 3.4.3 V	[125]

Dopant	Electrochemical Properties
K	217 mAh g−1 at 0.1 C; CR of 87.4% after 150 cycles at 1 C (2.8–4.6 V).	[134]
Zr	133.6 mAh g−1 after 100 cycles at 250 mA g−1 (2.5–4.6 V)	[135]
Fe	138.9 mAh g−1 at 1 C with CR of 88.4% at 1 C after 350 cycles (2.8–4.3 V)	[145]
Cu and Fe	Initial discharge 143 mAh g−1 at 10 C; 168 mAh g−1 after 100 cycles at 1 C (2.8–4.3 V)	[137]
Ti	179.6 mAh g−1 after 200 cycles at 1 C; CR at 97.4% (3.0–4.5 V)	[139]
Mn	174.0 mAh g−1 at 2 C, with CR of 81% after 900 cycles at 2 C (2.8–4.3 V)	[148]
Te (1 wt.%)	159.2 mAh g−1 at 10 C, 205 mAh g−1 at 1 C; CR of 81.4% after 100 cycles at 1 C (2.7–4.5 V)	[141]
Na	170.1 mAh g−1 at 1 C, CR of 90.7% after 200 cycles at 1 C (2.8–4.3 V)	[146]
Concentration gradient of Al	116mAh g−1 at 10 C, 214 mAh g−1 at 0.1 C (2.8–4.4 V) full cell: 195 mAh g−1 at 1 C with CR at 99% after 500 cycles (3–4.2 V)	[144]
Concentration gradient of Al	198.1 mAh g−1 at 0.1 C; CR of 70.9% after 500 cycles at 1 C (3–4.3 V)	[142]

Coating	Preparation	Electrochemical Performance	Ref.
Li2SiO3	Solvothermal method using Si(OC2H5)4 and LiOH	133 mAh g−1 after 52 cycles at current density of 100 mA g−1 in the voltage range 3.0–4.6 V	[178]
Li2TiO3	Nanobelts obtained from reaction between MC2O4·xH2O and Ti(OC4H9)4	150 mAh g−1 at 0.5 C in the voltage range 3.0–4.3 V; CR of 92% after 100 cycles at 2 C rate	[177]
Li3VO4 (3 wt.%)	Wet chemistry using V2O5 and LIOH·H2O	164 mAh g−1 at 0.1 C in the voltage range 2.0–4.3 V; CR of 83% after 100 cycles at 1 C rate	[179]
MoO3/Li2MoO4 (3 wt.%)	Dry coating method using (NH4)6Mo7O24·4H2O	200 mAh g−1 at 0.1 C rate in the voltage range 2.8–4.3 V; CR of 94.8% after 100 cycles at 1 C	[168]
Li3PO4	In situ coating in NH4H2PO4 solution	176 mAh g−1 at 0.1 C rate in the voltage range 2.9–4.2 V; CR of 89.6% after 250 cycles at 1 C	[180]
Li3PO4-PPy co-coating	Two-step: wet-coating for Li3PO4/chem. polymer. PPy	159 mAh g−1 at 10 C rate in the voltage range 2.8–4.5 V; CR of 95.1% after 50 cycles at 0.1 C	[194]
Li3PO4-AlPO4 co-coating	Al(H2PO4)3 added to ethyl alcohol	182.8 mAh g−1 at 1 C in the range 2.8–4.3 V; CR of 91.79% after 100 cycles at 1 C	[186]
Li3PO4-AlPO4-Al(PO3)3 coating	Al(PO3)3 in ethanol reacting with NCM811	201.8 mAh g−1 at 0.1 C in the range 3.0–4.3 V; CR of 85.4% after 50 cycles at 0.1 C	[187]
FePO4	Sol–gel method	151.4 mAh g−1 at 5 C in the voltage range 2.74–4.5 V; CR of 86% after 400 cycles at 0.2 C	[188]
LiAlF4	ALD	184 mAh g−1 at 50 mA g−1 in the voltage range 2.74–4.5 V; CR of 76% after 300 cycles	[181]
LiF-LaF3	Polyvinyl pyrrolidone-assisted wet coating process	173.6 mAh g−1 at 5 C in the voltage range 2.8–4.6 V; CR at 81.8% after 100 cycles at 5 C	[200]
SiO2	Aqueous solution method using Na2SiO3·9H2O	185 mAh g−1 at 1 C rate in the voltage range 2.8–4.3 V; CR of 90% after 300 cycles	[167]
LaAlO3 (3 wt.%)	Solid method, using La(NO3)3·6H2O and Al(CH(CH3)2O)3	155 mAh g−1 at 1 C rate in the voltage range 2.7–4.3 V; CR of 84.5% after 200 cycles at 1 C	[170]
LaPO4	Wet chemistry aqueous solution with La(NO3)3·6H2O + NH4H2PO4	200 mAh g−1 at 0.1 C rate in the voltage range 3.0–4.3 V; CR of 91.2% after 100 cycles at 1 C	[189]
AlPO4 (0.5 wt.%)	Ethyl alcoholic solution with Al(H2PO4)3 at 50 °C	150 mAh g−1 at 10 C rate	[186]
Co3O4 (0.6 wt.%)	Sonication in ethanol solution with Co(OH)2	186 mAh g−1 at 1 C rate after 100 cycles	[204]
WO3 (0.25 wt.%)	Wet process in alcohol using WO3 dissolved in H2O2	189 mAh g−1 at 0.2 C rate in the voltage range 2.8–4.3 V; CR of 70% after 100 cycles at 1 C	[169]
Li1.5Al0.5Zr1.5(PO4)3 (1 wt.%)	Sol–gel method	179.3 mAh g−1 at 1 C in the voltage range 2.8 4.5 V; CR at 84.8% after 200 cycles at 1 C	[201]
PANI-PEG	One step wet-coating method	156.7 mAh g−1 at 10 C in the voltage range 2.8–4.3 V; CR of 88.4% after 100 cycles at 2 C	[195]
PEDOT-coated LiNi0.85Co0.1Mn0.05O2	CVD process	178 mAh g−1 at 1 C rate in the voltage range 2.7–4.3 V; CR of 91% after 100 cycles at 1 C	[196]
Pyr-2D	Reaction of amine and ketone in presence of NCM	175 mAh g−1 at 1 C rate; CR of 88.8% after 100 cycles at 1 C; voltage range 2.8–4.5 V	[199]

Dopant	Electrochemical Properties
Zr	172 mAh g−1 at 1 C; Cr of 83.2 % after 200 cycles at 1 C (2.8–4.5 V)	[229]
Ti	165.02 mAh g−1 at 1 C; CR of 77.01% after 150 cycles at 1 C (2.8–4.3 V)	[233]
Ti	160.6 mAh g−1 after 200 cycles at 1 C; CR of 95.03% (2.8–4.3 V)	[234]
Al	154 mAh g−1 after 200 cycles at 1 C; CR of 85.32% (2.8–4.3 V)	[234]
Mg	147 mAh g−1 after 200 cycles at 1 C; CR of 82.07% (2.8–4.3 V)	[234]
Al	171.71 mA h g−1 at 1 C; CR of 96.15% after 100 cycles at 1 C (3.0–4.3 V)	[240]
Al-doped gradient	203 mAh g−1 at 0.5 C; CR of 95% after 100 cycles at 0.5 C CR of 95% after 1000 cycles at 1 C in full cell (graphite anode) (3.0–4.2 V)	[242]
Al-doped gradient	213.6 mAh g−1 at 0.1 C; Cr of 89.5% after 200 cycles at 0.1 C (3.0–4.5 V) 145 mAh g−1 at 10 C	[243]
P and F codoping	162.3 mAh g−1 after 100 cycles at 0.5 C, CR of 94.4% (3.0–4.3 V)	[250]
Y	189.4 mAh g−1 at 0.5 C; CR of 98.4% after 100 cycles at 0.5 C (2.8–4.5 V)	[255]
La	192 mAh g−1 at 1 C; CR of 90.1% after 200 cycles (2.75–4.5 V)	[256]

Author Contributions

Conceptualization, C.M.J. and A.M.; writing-review and editing, A.M. and C.M.J. All authors have read and agreed to the published version of the manuscript.

Funding

This research received no external funding.

Conflicts of Interest

The authors declare no conflict of interest.

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