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Review

Design and Synthesis Strategy of MXenes-Based Anode Materials for Sodium-Ion Batteries and Progress of First-Principles Research

by
Dan Su
1,
Hao Zhang
2,
Jiawei Zhang
1 and
Yingna Zhao
1,3,*
1
Hebei Province Laboratory of Inorganic Nonmetallic Materials, College of Material Science and Engineering, North China University of Science and Technology, Tangshan 063210, China
2
College of Clinical Medicine, North China University of Science and Technology, Tangshan 063210, China
3
Hebei (Tangshan) Ceramic Industry Technology Research Institute, Tangshan 063007, China
*
Author to whom correspondence should be addressed.
Molecules 2023, 28(17), 6292; https://doi.org/10.3390/molecules28176292
Submission received: 24 July 2023 / Revised: 16 August 2023 / Accepted: 24 August 2023 / Published: 28 August 2023
(This article belongs to the Special Issue Advanced Electrode Materials for Electrochemical Energy Storage and Conversion)
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Abstract

:
MXenes-based materials are considered to be one of the most promising electrode materials in the field of sodium-ion batteries due to their excellent flexibility, high conductivity and tuneable surface functional groups. However, MXenes often have severe self-agglomeration, low capacity and unsatisfactory durability, which affects their practical value. The design and synthesis of advanced heterostructures with advanced chemical structures and excellent electrochemical performance for sodium-ion batteries have been widely studied and developed in the field of energy storage devices. In this review, the design and synthesis strategies of MXenes-based sodium-ion battery anode materials and the influence of various synthesis strategies on the structure and properties of MXenes-based materials are comprehensively summarized. Then, the first-principles research progress of MXenes-based sodium-ion battery anode materials is summarized, and the relationship between the storage mechanism and structure of sodium-ion batteries and the electrochemical performance is revealed. Finally, the key challenges and future research directions of the current design and synthesis strategies and first principles of these MXenes-based sodium-ion battery anode materials are introduced.

Graphical Abstract

1. Introduction

In order to cope with the increasingly serious energy crisis and environmental pollution, people are gradually increasing the use of natural resources such as solar, wind and tidal energy; however, due to the complex distribution, discontinuity and other problems, people also need to find energy storage and conversion systems to convert these natural resources into clean energy that can be used by human beings continuously. Secondary batteries are an important class of energy storage devices. Since the commercialisation of lithium-ion batteries in 1991, they have played an important role in mobile electronics, electric vehicles and grid energy storage [1]. However, the high preparation cost, low energy density, and potential safety risks caused by organic electrolytes in lithium-ion batteries (LIBs) have triggered widespread concerns [2]; therefore, there is an urgent need to find alternative battery technologies for low-cost and high-safety applications to meet the stringent requirements of large-scale energy storage devices and a variety of consumer electronics products. Sodium-ion batteries have attracted great interest because they exhibit electrochemical properties similar to those of lithium-ion batteries, and sodium has the advantages of abundant reserves and low cost. However, compared with lithium, sodium has a larger ionic radius (0.102 nm), higher standard reduction potential (−2.71 V vs. standard hydrogen electrode (SHE)) and lower electronegativity (0.93), which leads to the fact that sodium-ion batteries always suffer from the slow adsorption and insertion of Na+ as well as a large volume expansion [3,4]. This results in sodium-ion batteries with a low reversible capacity and poor cycling stability, which limits the reversible capacity of sodium-ion batteries. The low reversible capacity and poor cycling stability of sodium-ion batteries limit their large-scale generation and use [5,6,7]. As a result, numerous researchers have focused on developing new sodium storage materials with tuneable chemical structures to improve sodium storage efficiency.
Since the successful exfoliation of graphene in 2004, two-dimensional (2D) materials have attracted great research interest due to their good properties, such as high electrochemical activity [8] and fast ion diffusion pathway [9]. In 2011, an emerging class of 2D materials, MXenes, was successfully prepared, and in the past 10 years, MXenes have been extensively studied, especially in the field of sodium-ion batteries. Extensive and in-depth research has been carried out on MXene materials, especially in the field of sodium-ion batteries. MXenes is a collective name for a class of 2D transition metal carbides or carbon-nitrides, whose general formula is denoted as Mn+1XnTx, where M denotes the transition metal element (Ti, Nb, Sc etc.), X is the carbon or nitrogen element and T denotes the terminal surface groups (-O,-F and -OH), which are mainly formed by the use of Hydrofluoric acid or a mixture of hydrochloric acid and lithium fluoride prepared by selective etching of A-layers (Al, Si, and Ga etc.) from the corresponding Mn+1XnTx phase [10,11,12]. The highly conductive 2D lamellar structure [13] and tuneable surface chemistry [14] of MXene materials allow them to offer new possibilities as anode materials in solving the problems of slow Na+ diffusion rate and high diffusion barriers in sodium-ion batteries. However, the collapse and re-stacking of MXene lamellae hinder the full utilisation of MXenes’ active sites and limit the large-scale application of MXenes as anodes for sodium-ion batteries. Therefore, numerous researchers have promoted the further practical application of MXene materials in the field of energy storage devices by designing MXenes-based materials that can significantly increase the electronic conductivity and enhance their electrochemical performance while preventing the aggregation of individual nanosheets [15].
Since 2015, MXenes-based materials have developed rapidly in the field of energy storage, and a large number of research articles on sodium-ion batteries have been published. In this review, we first summarise the research work and development in the field of MXenes-based sodium-ion energy storage materials in recent years, focusing on the design and synthesis strategies of MXenes-based sodium-ion battery anode materials currently employed by, and in particular illustrating the effects of, the various design strategies on the structure and properties of MXenes-based materials, as shown in Table 1. On this basis, we also summarise the recent first-principles study of MXenes-based anode materials for sodium-ion batteries to reveal the storage mechanism and the relationship between the structure and electrochemical performance of sodium-ion batteries. Finally, the current challenges and future directions of the design and synthesis strategies and first-principles studies of MXene-based anode materials for sodium-ion batteries are summarised and outlined.

2. Design and Synthesis Strategy of Anode Materials for MXenes-Based Sodium-Ion Batteries

Although MXenes as an emerging anode material for sodium-ion batteries have attracted great research interest, their tendency to aggregate or stack in practical use greatly hinders electron transport, leading to their own low capacity and further limiting the large-scale application of MXenes. In order to solve these problems, researchers have proposed a number of design and synthesis strategies, which we summarise as elemental doping modification, binary material composite and ternary material composite.

2.1. Design and Synthesis of Elementally-Doped MXenes-Based Materials

Elemental doping modification of MXene materials is one of the most common strategies employed by researchers to dope heteroatoms such as nitrogen (N) and sulphur (S) onto carbon-based materials [16] in order to enhance material specificity. Based on the conventional preparation of sulphur-doped multilayer Ti3C2Tx MXene, Bao et al. [17] prepared sulphur-doped Ti3C2Tx MXene (S-Ti3C2Tx) with a 3D folded structure by employing a vacuum freeze-drying method (Figure 1A). The reduction and oxidation peaks of the negative electrodes of the S-Ti3C2Tx have a small potential difference between the reduced and oxidised peaks, and the enlarged interlayer spacing of the MXene leads to the electrodes with good dynamic properties. Its initial discharge capacity reached 970 mAh g−1, and the discharge capacity was maintained at 690.3 mAh g−1 after 200 cycles with a decay rate of 0.14% per cycle (Figure 1B). The capacity was maintained at 577.1 mAh g−1 after 500 cycles at 2C (Figure 1C). Sun et al. [18] produced sulphur-doped Ti3C2 MXenes by electrostatic self-assembly (Figure 1D), and the capacity of the electrodes of this material was 135 mAh g−1 after 1000 cycles at a current density of 2 A g−1, with an average capacity loss of only 0.033% per cycle. The average capacity loss per cycle was only 0.033%. The heat treatment temperature also has a certain effect on the elemental doping modification, and the S-doped MXene electrode has a larger interlayer spacing and more abundant active sites at high temperature [19]. Li et al. [20] used sulphur as a template to modulate the surface chemistry and microstructure of Ti3C2 calcined at 400 °C to obtain the mesoporous thin film of Ti3C2Tx (SMX-100), and the results of electrochemical studies showed that the electrode still maintained a stable specific capacity of 206.2 mAh g−1 after 200 cycles at 100 mA g−1 (Figure 1E), and the SMX-100 electrode consistently maintained a high capacitance during the charge/discharge cycling process (Figure 1F), which was mainly due to the effective penetration of the electrolyte and the increase in the layer spacing caused by the insertion of Na+. The results show that the incorporation of sulphur terminals can significantly accelerate the redox reactivity of Na–S cells and limit the outward diffusion of polysulfides, so that Na–S cells have higher rate capability.
Nitrogen doping has been shown to be one of the facile modification strategies to improve the electrochemical properties of MXenes [21,22,23]; however, the position of nitrogen doping has an effect on the electrical properties of MXenes due to the underlying mechanism. Jin et al. [24] synthesised Ti3C2 MXenes (SWMP-5) with sandwich structure by using the interfacial self-assembly method to ultrasonicate Ti3C2 in poly(vinyl imine) solution (Figure 2A). The dense N-rich polymer with a hydrogen bonding network connects the stable conductive framework to provide a fast channel for Na storage. The SWMP-5 negative electrode has an initial discharge capacity of 338.5 mAh g−1 (Figure 2B), and provides excellent multiplicative rates of 224.5, 185, 161, 141, 120, and 105 mAh g−1 at current densities ranging from 50–2000 mA g−1 capacity (Figure 2C). Fan et al. [25] used poly(melamine) microspheres as templates to treat Ti3C2 to obtain N-Ti3C2Tx (M8T1) with a highly uniform and well-defined porous framework structure (Figure 2D). The average capacity reaches 180.5 mAh g−1 (Figure 2E) at a current density of 25 C (1 C = 200 mA g−1), while the capacity retention after 3500 cycles at a current density of 2 A g−1 is 75% (Figure 2F), showing good cycling stability. The sodium-ion storage mechanism demonstrates that the interconnected nanosheets have a porous skeleton structure and high electronic conductivity, forming continuous conductive structures and creating multi-dimensional ion channels, which is conducive to rapid ion diffusion. The above studies show that surface modification of nitrogen atoms can greatly enhance the electrochemical reactivity and electronic conductivity of materials, and nitrogen doping strategies can induce well-defined porous structure, high surface area and macroporous volume. However, due to the influence of the underlying mechanism, the position of nitrogen doping has a certain influence on the electrical properties of MXenes, and the current research on its position is not comprehensive enough, so further research is still needed.

2.2. Design of MXenes-Based Binary Composite Synthesis

Compared with elemental doping, the design of- composite systems for MXenes can better solve the problems of slow ion transport due to the large radius of Na+ and volume expansion during electrochemical sodiation/desodiation [26,27,28]. Therefore, numerous researchers have focused on the design of MXenes-based binary composites to promote the embedding and de-embedding of Na+ during the electrochemical process of sodium-ion batteries and to improve the structural durability of the anode of sodium-ion batteries by constructing a binary heterojunction structure, which enhances the relevant performance of sodium-ion batteries. However, different preparation methods will not only affect the interaction between the second phase and MXenes, but also affect the morphology and properties of the composite. In this regard, we summarise the above adopted strategies as hydrothermal or solvent-thermal methods, electrostatic self-assembly methods, in situ synthesis methods and methods such as CVD.

2.2.1. Hydrothermal Methods

The hydrothermal method is one of the most commonly used methods for the preparation of MXenes-based sodium-ion battery anode materials due to its advantages of easy preparation of nanomaterials with good crystallinity and different shapes and sizes. Wu et al. [29] prepared flower-like three-dimensional VO2/MXenes sodium-ion battery anode materials in different proportions (Figure 3B) by using the hydrothermal method (Figure 3A) with a 0.1 A g−1 current density after 200 cycles with a reversible capacity of 280.9 mAh g−1 (Figure 3C). Sun et al. [30] obtained NTO/Ti3C2 layered material with a porous structure on the basis of the MXenes’ stabilised structure by a two-step hydrothermal method (Figure 3D), and the composite material, after 1900 cycles at a current density of 2000 mA g−1, still provides a reversible capacity of 82 mAh g−1 (Figure 3E), which shows excellent stability.
Although the hydrothermal method is simple to operate and can produce a variety of novel and unique morphologies, there are still a series of shortcomings, such as high equipment requirements, long reaction time and high energy consumption. Based on this, more and more researchers are optimizing the hydrothermal method by combining two different preparation methods. Consequently, researchers have improved the hydrothermal method and combined it with other treatments to jointly prepare MXenes-based binary composites with better electrochemical properties, e.g., Xu et al. [31] used a simple hydrothermal method combined with a heat treatment process under H2 atmosphere to prepare a novel MoSe2/MXenes heterojunction ultrafast kinetic network electrode (Figure 3F). Afterwards, Zhang et al. [32] prepared SnS nanoparticle-modified Ti3C2Tx composites using a similar process (Figure 3G). The first-time charge/discharge capacities of SnS/Ti3C2Tx were 348.4 and 495.0 mAh g−1 (Figure 3I) with a coulombic efficiency of 70.4% (Figure 3H), and at a high current density of 1000 mA g−1. The discharge capacity was still maintained at 255.9 mAh g−1, and the reversible discharge capacity after 50 cycles at a current density of 500 mA g−1 was about 320 mAh g−1 with a Coulombic efficiency of 98% (Figure 3J). The use of CoNiO2, CoNi2O4, NiCo2O4, CoNi2S4 and other polytransition metal materials with high theoretical capacity and excellent electrical conductivity to enhance the electrochemical performance of MXene materials has also been an area of intense focus in recent years. Tao et al. [33] obtained CoNiO2/MXenes composites through the combination of the hydrothermal method and a heat treatment process, the first-time capacity of the material was 463 mAh g−1 and its reversible capacity reached 248.1 mAh g−1 in the charging/discharging experiment at 100 mA g−1. The good electrochemical performance of the CoNiO2/Ti3C2Tx composites is attributed to the increase in electrochemically active sites by the nano-CoNiO2 which shortens the diffusion paths of Na+ during the cycling process. Nevertheless, the long reaction time, complicated operation and high production cost of the hydrothermal method limits its use in large-scale production.

2.2.2. Electrostatic Assembly Method

The self-assembly [34] method of electrochemical modification of the material surface has attracted much attention in the field of energy storage devices due to its simplicity, environmental friendliness, high efficiency, and low cost. Liu et al. [35] assembled VO2 nanotubes (VO2-NTs) and Ti3C2Tx MXenes into a multidimensional crosslinked structure of VO2-NTs/Ti3C2 anodes via electrostatic assembly. Xie et al. [36] prepared porous Ti3C2Tx/CNTs composite thin films by electrostatic assembly combined with the chemical vapour deposition (CVD) method, which effectively prevented MXenes from being grafted in the structure. They also used the deposition (CVD) method to prepare porous Ti3C2Tx/CNTs composite films, in which the grafted carbon nanotube CNTs in the structure effectively prevented the refolding of the MXene nanosheets and formed a porous structure, which facilitated the transport of the electrolyte and the access of ions to the electrodes. Zhao et al. [37] designed a novel molecular level PDDA-BP/Ti3C2 nanosheet heterostructure, which effectively discharged for more than 6 h to reach 3.0 V after 60 s of charging using a light-emitting diode (LED). Wu et al. [38], using the unique adsorption behaviours of oxygen-containing functional groups, produced MXenes that were self-assembled with SnS2 by vacuum-assisted filtration to obtain MXenes/SnS2 composites with different ratios (Figure 4A,B). The first charge/discharge capacities of the composites (MXenes/SnS2 = 5:1) at a current density of 100 mA g−1 were 460 mAh g−1 and 882 mAh g−1, respectively (Figure 4C), and the reversible capacity reached 322 mAh g−1 after 200 cycles (Figure 4D). In addition to the common lamellar MXenes-based composites, researchers have also constructed MXenes-based composites with a variety of microscopic morphologies, e.g., Dong et al. [39] used an in situ electrostatic attraction and selenide process to homogeneously anchor Ni0.5Co0.5Se2 nanoparticles to Ti3C2Tx conductive structures and prepared structurally stable Ni0.5Co0.5Se2/Ti3C2Tx composites (Figure 4E). Guo et al. [40] also prepared MXenes Ti3C2Tx nanosheet-encapsulated titanium oxide sphere structures (TiO2@Ti3C2Tx) for the first time by using a self-assembly strategy (Figure 4F), and the MXene layer with high electronic conductivity protects the TiO2 spheres from electrochemical comminution, forming a stable solid-electrolyte interface. Although the electrostatic self-assembly technology is developing rapidly at present, there are some problems in its theoretical and practical applications, which urgently need to be further solved by researchers.

2.2.3. In Situ Synthesis Method

There are certain problems in the composite materials prepared by the adhesion method, such as the disadvantages of the introduced particle size, unstable thermodynamic properties and low interfacial bonding strength. Such problems can be ameliorated by in situ growth within the matrix through chemical reactions. In recent years, it has become one of the research hotspots to use in situ synthesis technology with the advantages of stable thermodynamic properties, non-polluting interfaces and high bonding strength to prepare MXenes-based binary composite anode materials, which are suitable for the construction of high-performance sodium-ion rechargeable batteries. Tang et al. [41] successfully prepared M-SnP-In composites through the growth of ultra-small SnO2 nanoparticles (NPs) in the intermediate layer of Ti3C2Tx composites (Figure 5A,B), and the M-SnP-In electrode maintained a high capacity of 436.6 mAh g−1 after 1500 cycles at a current density of 2A g−1 (Figure 5C), which is superior to most sodium-ion batteries reported so far. Ding et al. [42] successfully prepared FePS3@MXenes 2D/2D heterojunction composites by in situ mixing of ultrathin MXene nanosheets with FePS3 nanosheets (Figure 5D,E), and Ming et al. [43] prepared NaTiO2 nanotubes (NTO NTs) on Ti3C2Fx in situ as the enhanced sodium-ion battery. The NTO NTs were grown vertically on the Ti3C2Fx layer, which promoted Na+ diffusion and electron transfer and effectively inhibited the aggregation of the Ti3C2Fx layer. Zhang et al. [44] proposed a silver-ear-like carbon coated Ti3C2Tx (T-MXenes@C) anode material for sodium-ion batteries (Figure 5F,G). Self-polymerisation of dopamine on pristine Ti3C2Tx nanosheets effectively promoted the transformation of Ti3C2Tx into a silver-ear-like 3D structure, which was then carbonised in inert air to form a thin carbon coating that would protect the exposed surface of the Ti3C2Tx nanosheets from air oxidation and structural aggregation. The 3D silver-ear-like structure with active and stable surface (T-MXene@C) promotes charge transport, improved multiplicity performance and long cycling performance, among others. Despite the advantages of the in situ synthesis method, more in-depth studies on its reaction mechanism, practical applications and process optimisation are still needed to provide new possibilities for its industrial production.
Although the in situ synthesis method has many advantages, most of the in situ reaction systems are still in the stage of experimentation and development research, and the in situ reaction process is not easy to control, and the formation of intermediate phases cannot be controlled, which adversely affects the properties of materials. The content and ratio of reactants have a great influence on the formation of the reaction and the reaction speed, and it is difficult to control. It is still necessary to carry out more in-depth research on its reaction mechanism, practical application and process optimization to provide new possibilities for its industrial production.

2.2.4. Other Synthesis Strategies

In addition to the synthetic methods involved above, there are some other synthetic strategies to prepare MXenes-based binary composite sodium-ion battery anode materials [45,46], such as chemical vapour deposition (CVD) and anodic oxidation. Shen et al. [47] successfully synthesised TiC/C core/shell nanowire arrays on Ti6Al4V substrates using a modified one-step chemical vapour deposition (CVD) method. The prepared TiC/C nanowire arrays have a core/shell structure and a porous structure, which increase the contact and active area, provide good buffering capacity against volume changes, and enable fast electron/ion transfer. Zhang et al. [48] successfully synthesised amorphous vanadium oxide/V2C MXenes (a-VOx/V2C) nano by anodic oxidation of multilayers of V2CTx at a constant voltage in aqueous electrolyte hybrids. The reversible capacity was as high as 307 mAh g−1 at 50 mA g −1, and the multiplicative capacity was as high as 96 mAh g−1 at 2000 mA g−1.

2.3. Design and Synthesis of MXene-Based Ternary Composites

Based on the synthetic basis of MXenes-based binary composites, researchers have designed and constructed MXenes-based ternary composites in anticipation of obtaining anode materials for sodium-ion batteries with better electrochemical properties. Cao et al. [49] then designed a unique microbial electrostatic assembly method based on the traditional electrostatic assembly method and prepared a 2D transition metal sulphide-MXene-carbon-based nanoribbon with heterogeneous structured negative electrodes (Figure 6A). This method promotes the migration and stable storage of high-capacity Na+ by constructing a heterojunction interface with multiple surface-active sites and highly conductive main chain structure, effectively alleviating the slow kinetics of sodium-ion batteries. However, the performance of MXenes-based composites prepared by a single synthesis process often fails to reach the expectation, and multiple preparation methods also need to be used together. Yuan et al. [50] used the template method and the electrostatic assembly method to prepare the Nb2CTx/MoS2@CS ternary composites, which had a specific capacity of 394 mAh g−1, with 74.1% capacity retention after 900 cycles at a current density of 1 A g−1, with good capacity stability (Figure 6B). Li et al. [51] combined the in situ growth method and template method to assemble Ti3C2Tx MXene nanosheets into thin-walled hollow spheres using PMMA spheres as sacrificial templates (Figure 6C), and then N-doped CoS2 nanoparticles embedded in them were grown to obtain MXene@CoS2/NC ternary composites. The electrochemical performance test shows that it has a high initial discharge capacity of 355 mAh g−1 and the capacity retention rate is around 100% after 5000 cycles (Figure 6D).
In addition to common preparation methods, some new synthesis processes have been gradually developed, and Wang et al. [52] innovatively proposed the preparation of a 3D printed V2CTx/rGO-CNT anode (Figure 6E). The hierarchical and porous 3D structure of this ternary composite not only maintains the relative integrity of the entire electrode structure, but also provides abundant active sites to enhance the Na ion/electron transport kinetics of sodium-ion batteries. Electrochemical performance tests showed that the anode material could maintain stable cycling for 3000 h at 2 mA cm−2 and 10 mAh cm−2 with an average Coulombic efficiency of 99.54%, as well as stable operation for 1000 h at high current densities of 5 mA cm−2 and 50 mAh cm−2. Fang et al. [53] have also used the novel synthesis processes-coating method and melt-infusion method to obtain Na-Ti3C2Tx-CC ternary composites (Figure 6F). The composites have good anti-viscosity and machinability, which verifies the feasibility of producing flexible Na-metal electrodes and provides new possibilities to promote the practical application of sodium-ion batteries.
Table 1. Comparison of physical properties of MXene-based materials.
Table 1. Comparison of physical properties of MXene-based materials.
Serial NumberMaterial CompositionPreparation MethodFirst Charge (mAh g−1)First Discharge (mAh g−1)Cycling PerformanceRate CapabilityReferences
1S-doped Ti3C2TxVacuum freeze drying821.7970577 mAh g−1 after 500 cycles [17]
2S-doped Ti3C2TxElectrostatic self-assembly 325135 mAh g−1 after 1000 cycles at 2.0 A g−1136.6 mAh g−1 at 5 A g−1[18]
3S-doped mesoporous Ti3C2Tx filmElectrostatic self-assembly 354.6345.6 mAh cm−3 after 5000 cycles at 1 A g−1129.2 m Ah g−1 at 1 A g−1[20]
4N-doped Ti3C2TxElectrostatic self-assembly132.6338.5123.4 mAh g−1 after 5000 cycles at 1 A g−1120 mAh g−1 at 1 A g−1[24]
5N-doped Ti3C2TxElectrostatic self-assembly 1844.7284.2 mAh g−1 after 1000 cycles at 5.0 C180.5 mAh g−1at 25 C[25]
6VO2/MXenesHydrothermal method 229.2280.9 mAh g−1 after 200 cycles at 0.1 A g−1206 mAh g−1 at 1.6 A g−1[29]
7NaTi8O13/NaTiO2Two-step hydrothermal method12516282 mAh g−1 after 1900 cycles at 2.0 A g−1143 mAh g−1 at 0.1 A g−1[30]
8MoSe2/MXeneHydrothermal method combined with thermal annealing process578826384 mAh g−1 after 400 cycles at 2.0A g−1490 mAh g−1 at 1.0A g−1[31]
9SnS/Ti3C2TxHydrothermal method combined with thermal annealing process348.4495.0320 mAg−1 after 50 cycles at 500 mAg−1255.9 mAh g−1 at 1000 mA g−1[32]
10CoNiO2/MXeneHydrothermal method combined with thermal annealing process 463223 mAh g−1 after 140 cycles at 0.1 A g−1188 mAh g−1 at 0.3 A g−1[33]
11VO2-NTs/Ti3C2Electrostatic self-assembly11642132516 mAh g−1 after 2000 cycles at 5.0 A g−1703 mAh g−1 at 10.0 A g−1[35]
12Ti3C2Tx/CNTElectrostatic self-assembly179501120 mAh g−1 after 500 cycles at 0.1 A g−1 [36]
13PDDA-BP/Ti3C2Electrostatic self-assembly178025881112 mAh g−1 after 500 cycles at 0.1 A g−1560 mAh g−1 at 1 A g−1[37]
14TiO2@Ti3C2TxElectrostatic self-assembly233.9497.1116 mAh g−1 after 5000 cycles at 0.96 A g−1177 mAh g−1 at 0.12 A g−1[40]
15M-SnP-InIn situ synthesis 438.2436.6 mAhg−1 after 1500 cycles at 2 Ag−1438.2 mAhg−1 at 15 A g−1[41]
16T-MXene@CIn situ synthesis580.6 499.4 mAh g−1 after 200 cycles at 0.2 C478 mAh g−1 at 0.2 C (1 C = 320 mA g−1)[44]
17a-VOx/V2CIn situ synthesis 16154 mAh g−1 after 1800 cycles at 2000 mA g−196 mAh g−1 at 2 Ah g−1[48]
18Cu1.75Se—MXene—CNRibMicrobial electrostatic assembly744.21353.1305.6 mAh g−1 after 400 cycles at 1.0 A g−1435.3, 356.2, 315.7, 274.3, 232.6, and 161.3 mAh g−1 at 0.1 to 5.0 A g−1[49]
19Nb2CTx/MoS2/CSElectrostatic self-assembly method + template method 1270526 mAh g−1 after 100 cycles at 0.1 A g−1
394 mAh g−1 after 900 cycles at 1 A g−1		196 mAh g−1 at 20 A g−1[50]
20MXene@CoS2/NCIn situ growth method + template method660885620 mAhg−1 after 200 cycles at 0.2 A g−1708, 614, 551, 438, and 394 mAh g−1 at 0.2, 0.5, 1, 2, and 5 A g−1[51]

3. First-Principles Study of Anode Materials for MXenes-Based Sodium-Ion Batteries

The first principles based on density functional theory can simulate the kinetics of electrochemical reactions from the atomic level, which helps to understand and analyse the relevant energy storage mechanism of battery materials, and also provides a theoretical basis for the design of new battery materials, which is one of the important research tools in the field of energy storage devices. In the research process of MXenes-based anode materials for sodium-ion batteries, many researchers have conducted many studies on the electronic structure of MXene materials, the structure and physical and chemical properties of element-doped MXene materials and MXenes-based composites before and after modification, which have made great contributions to the understanding of the role of MXene materials in sodium-ion batteries.
All first-principles calculations were performed by the Vienna Ab initio Simulation Package (VASP). We chose projected-augmented-wave method (PAW) to describe the electron-ion interaction. The exchange–correlation interaction functional is the generalized gradient approximation (GGA) in the Perdew–Burke–Ernzerhof (PBE) functional.

3.1. MXenes Theoretical Computational Study of the Electronic Structure of the Material

Er et al. [54] conducted a first-principles study of the electronic structure of sodium ions on Ti3C2 in order to understand the differences in their adsorption on Ti3C2. Through the calculation of Na adsorption energy (Figure 7A), the adsorption energy was found to be only 4.40 eV, and combined with the results of density of states simulation of Ti3C2 before and after Na adsorption, the diffusion barrier of Na+ was 0.096 eV (Figure 7B), which indicated that Ti3C2 is a promising anode material for sodium-ion batteries. The basic mechanism for the MXene column effect to enhance the electrode performance of sodium-ion batteries is still unclear; based on this, Dai et al. [55] investigated the effects of different MXene interlayer stacking methods on the adsorption, diffusion and mechanical properties of Na atoms by employing the first nature principle with two typical MXenes as the research objects. It was found that for both Ti3C2O2 and Ti2CO2 configurations, the diffusion energy barriers of Na were greatly reduced when the C-Ti stacking mode was adopted (Figure 7C,D). This provides a useful theoretical basis for understanding the MXene column effect and contributes to the development of anode materials for sodium-ion batteries. This was followed by a first-principles study of the Na storage capacity of Ti3C2Tx by Bai et al. [56], which, after comprehensive calculations for all configurations of Eads2, extended the calculations to their theoretical capacities and obtained the optimal capacity-to-structure ratios in the stacked structure. The calculated CMNa value can be increased from 218.32 mAh g−1 to 413.13 mAh g−1, which is in good agreement with the previously reported value of 413.0 mAh g−1. The analysis of the optimal capacity-to-structure ratio shows that the increase in layer spacing favours the increase in MXene capacity, which provides a theoretical basis for achieving high-capacity sodium storage behaviour.

3.2. Theoretical Computational Study of Elementally Doped MXenes Materials

Using elemental doping as one of the common modification means, researchers have carried out a lot of studies on the first nature principle of elementally doped MXene materials. Bao et al. [17] experimentally demonstrated that the S-modified Ti3C2 material has a strong adsorption of Na2Sn in the Na–S cell. Based on this, Lu et al. [57] used a first-principles simulation to calculate the chemical properties and bond strengths between S-modified Ti3C2 and Na2Sen, which showed that S-doped Ti3C2 has strong anchoring and trapping effects on Na2Sen (Figure 8A). S-doped MXenes not only improve the chemical bonding energy and van der Waals force on Na2Sen, but also, more importantly, the joint action of S-doped MXene materials and the nano-scaled Na2Sen together can maximize the surface or near-surface charge storage of MXene materials, which is conducive to improving the charging and discharging capacity of sodium-ion batteries. Wang et al. [58], on the other hand, systematically investigated the performance of sulphur-functionalized MXenes as anode materials for sodium-ion batteries. The structural, kinetic and electronic properties of S-functionalized Ti2C single molecule membranes (Ti2CS2) were comprehensively investigated by first-principles calculations. The results show that the Ti2CS2 monolayers have not only good kinetic stability, but also metallic properties, thus ensuring excellent structural stability and electronic conductivity. Meanwhile the low diffusion barrier of Na+ and multilayer stable adsorption ensure the excellent capacity of Ti2CS2 monolayers in sodium-ion (935.57 mAh g−1) batteries, which is a theoretical basis for the design of high-capacity sodium-ion batteries. Liao et al. [59] investigated the effect of N doping on the electrical conductivity of Ti2C and Ti3C2 MXene materials before and after N doping using first-principles calculations. The results show that N doping can significantly improve the electrical conductivity of Ti2C and Ti3C2 (Figure 8B), while both Ti2C and Ti3C2 exhibit metallicity at different N doping concentrations, which offers the possibility of their further application in sodium-ion batteries. In order to achieve the performance of fast charging and long cycling in sodium-ion batteries, Xia et al. [60] explored the effect of N doping on the electronic structure of Ti3C2 using first-principles calculations. The results show that N atom doping induces charge redistribution and the formation of active sites in the MXene material, and at the same time improves the electronic conductivity of Ti3C2O1.83N0.17,which suggests the feasibility of realising high-performance sodium-ion electrodes based on the MXene material at room temperature.
In addition to the common studies on N and S-element-doped MXene materials, researchers have also investigated the first principles of other element-doped MXene materials. Zhao et al. [37] investigated the relaxation process when Na was added to the surface functional groups (-F, -O, and -OH), and by comparing the binding energy as well as the charge densities (Figure 8C), the researchers found that the intercalated Na+ first binds to the BP nanoparticles and then undergoes mixed adsorption on -F, -O and -P, which consequently reduces the binding energy and thus facilitates the diffusion of Na+ and charge transfer. Kajiyama et al. [61] have revealed that Ti3C2Tx exhibits a reversible Na+ embedding/de-embedding behaviour into/from the interlayer space in the non-Na+ electrolyte without a structural reason for the structural changes. The interlayer distance was maintained throughout the sodiation/desorption process due to the column-supporting effect of the captured Na+ and the swelling effect of the permeated solvent molecules between the Ti3C2Tx sheets, achieving reversible embedding/de-embedding of Na+, and thus no substantial structural changes occurred during the electrochemical reaction. For these reasons, Ti3C2Tx shows good capacity retention as well as excellent multiplicity in 100 cycles (Figure 8D), making it a promising anode material for sodium-ion batteries.

3.3. Theoretical Computational Study of MXenes Matrix Composites

Composite modification of MXene materials is also a good means of enhancing the properties, so many researchers have also focused on first-principles-related studies on MXenes-based composites. Zhao et al. [37] studied the interaction between Na and BP nanoparticles by first-principles calculations, and found that the interaction between Na and BP nanoparticles was significantly altered by comparing the Na-BP system and the PDDA-BP/Ti3C2 system before and after the relaxation process in terms of conformation, binding energy and charge density, it was found that Ti3C2 nanosheets significantly changed the sodic state of BP nanoparticles, which made it easier for them to obtain electrons from Na, facilitated the sodic process, and improved the sodium storage performance of the MXenes-based anode materials. Cao et al. [49] have conducted first-principles computational studies on the diffusion at the interface of MSe-MXenes-CNRib heterostructure behaviour, which was investigated by first-principles calculations. By studying the density of states of the ternary heterostructure, the adsorption energy, the difference in charge distribution of the Na adsorption heterostructure, and the energy distribution state of diffusion, it was not only confirmed that the synergistic effect would promote the adsorption and diffusion of Na ions to a certain extent, but it was also found that the heterostructure was capable of high-capacity storage of Na ions under different multiplicity conditions. Liu et al. [35] created a rational construction of the MXenes-based composite system based on the density functional theory, and the VO2 nanotubes (VO2-NTs) and Ti3C2Tx MXenes were composed into the VO2-NTs/Ti3C2 negative electrode material with a multidimensional cross-linking structure. Relevant theoretical calculations show that the rich multidimensional channels of the composite reduce the diffusion impedance of Na+, while the enhanced intrinsic conductivity and highly rigid structure solve the problems of poor cycling stability and multiplicity performance of VO2 due to the large volume change, which promotes the further practical application of sodium-ion batteries.

4. Conclusions

This review summarises the research efforts and developments in recent years on the design and synthesis strategies as well as first-principles studies of MXenes-based anode materials for sodium-ion batteries, detailing their numerous achievements in the field of sodium-ion batteries, and providing new possibilities for promoting the further practicalisation of sodium-ion batteries. In spite of the great progress made, there are still several key issues that have not been resolved in the research on the design and synthesis strategies and first principles of MXene-based anode materials for sodium-ion batteries, as shown below:
(1) Currently, the main method to obtain MXenes is still acid etching, which is characterised by low yield and high risk. Therefore, there is an urgent need for environmentally friendly, safe, efficient and high-quality methods, such as CVD or PVD, to synthesize MXenes with a controllable number of layers, adjustable surface groups, increased layer spacing and excellent quality. In addition, there is a need to optimize the existing synthesis methods and conduct in-depth research on the generation mechanism, which can be used to promote the practical large-scale industrial production of MXenes and MXenes-based materials.
(2) As mentioned earlier, the surface chemistry of MXenes may significantly affect the properties of MXenes-based materials. Different etchants can produce groups with different surface chemistries, but the precise surface chemistry of MXenes and the interactions between the surface groups and the materials are still not well understood. In addition, it was shown that bare/-O capped MXenes have better physicochemical properties. Therefore, more studies are needed to modulate the surface chemistry and explore its application in electrochemical storage.
(3) Another major problem with MXenes is their stability. The interlayer structure of an MXene is unstable under room temperature conditions, which can easily lead to the problem of heavy stacking, which seriously hinders the long-term development of MXenes-based materials. To alleviate this situation, efforts can be focused on rational structural design and precise morphological control of electrodes, such as 3D porous structure, aerogel and coating technology.
(4) Theoretical studies must take into account the inhomogeneous and incomplete mixed coverage of surface groups and MXene-stacked multilayers in order to accurately predict their properties and thus guide experiments. It is thus necessary to combine theoretical calculations with advanced computations, including machine learning, classical molecular dynamics and high-throughput calculations, to fully understand the surface chemistry and interfaces of MXenes-based materials. In addition, relevant theoretical models as well as computational software and hardware should be further developed to narrow the gap between theoretical predictions and experimental results.
In summary, MXenes are one of the electrode materials with great potential for development in the field of energy storage devices, but they still face great challenges in moving from the laboratory research stage to the industrial application stage. This requires researchers to conduct sufficient practical studies to improve the knowledge and understanding of this class of materials in order to explore and exploit its material advantages and to promote the commercial application of MXenes.

Author Contributions

D.S. was responsible for most of the work, such as writing the main content of the article, drawing, and data inquiry; H.Z. made a summary and statistical analysis of the progress of relevant materials. He applied statistics and other techniques to analyse or synthesize the characteristic information of the research materials, guided and gave the main line of the review, and as the co-author of the article, he made significant contributions to the large length of the article summary and the progress of the timeline; J.Z. was responsible for part of the content writing, drawing and data query. Y.Z. was responsible for the idea of the entire paper, paper revision and other work. All authors have read and agreed to the published version of the manuscript.

Funding

This work was financially supported by the Hebei Province Natural Science Foundation of Iron and Steel Joint Fund: (No. E2021209002), and it was also supported by Project of Tangshan Science and Technology Bureau (No. 21130211D, 22130215H).

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

All relevant data are provided in the article.

Conflicts of Interest

The authors declare no conflict of interest.

Sample Availability

Not applicable.

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Figure 1. (A) Schematic diagram demonstrating the preparation of sulphur-doped MXene [17]. (B) Cycling performances of S-Ti3C2Tx/S electrode and bare Ti3C2Tx/S electrode at 0.5 C for 200 cycles [17]. (C) Cycling performances of S-Ti3C2Tx/S cathode and bare Ti3C2Tx/S cathode at 2 C for 500 cycles [17]. (D) Schematic illustration of the preparation of sulphur-decorated Ti3C2 MXenes [18]. (E) Cycling performances of SMX-100 at 0.1 A g−1 [20]. (F) Charge–discharge curves at different current densities [20].
Figure 1. (A) Schematic diagram demonstrating the preparation of sulphur-doped MXene [17]. (B) Cycling performances of S-Ti3C2Tx/S electrode and bare Ti3C2Tx/S electrode at 0.5 C for 200 cycles [17]. (C) Cycling performances of S-Ti3C2Tx/S cathode and bare Ti3C2Tx/S cathode at 2 C for 500 cycles [17]. (D) Schematic illustration of the preparation of sulphur-decorated Ti3C2 MXenes [18]. (E) Cycling performances of SMX-100 at 0.1 A g−1 [20]. (F) Charge–discharge curves at different current densities [20].
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Figure 2. (A) Schematic illustration of the interfacial self-assembly MXene-based sandwich-like structure with polymer network [24]. (B) The initial and fiftieth cycle of galvanostatic charge/discharge curves of SWMP-5 and Ti3C2Tx MXene at 500 mA g−1 [24]. (C) Rate performance of SWMP-5 [24]. (D) SEM images of N-Ti3C2Tx (M8T1). (E) Rate performances of M8T1[25]. (F) Cycling performance of the 3D-printed SIC (SIC-4) at 2 A g−1. Inset: Real photo showing a 3D-printed woodpile N-Ti3C2Tx electrode [25].
Figure 2. (A) Schematic illustration of the interfacial self-assembly MXene-based sandwich-like structure with polymer network [24]. (B) The initial and fiftieth cycle of galvanostatic charge/discharge curves of SWMP-5 and Ti3C2Tx MXene at 500 mA g−1 [24]. (C) Rate performance of SWMP-5 [24]. (D) SEM images of N-Ti3C2Tx (M8T1). (E) Rate performances of M8T1[25]. (F) Cycling performance of the 3D-printed SIC (SIC-4) at 2 A g−1. Inset: Real photo showing a 3D-printed woodpile N-Ti3C2Tx electrode [25].
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Figure 3. (A) Schematic illustration of the synthetic process for VO2/MXenes hybrids [29]. (B) SEM images of the VO2/MX-1[29]. (C) Cyclic performances of VO2/MX, VO2 and MX at a current of 0.1 A g−1 [29]. (D) Schematic illustration for synthesizing the NTO/Ti3C2 composite [30]. (E) Long-term cycling performance and CE data of the NTO/Ti3C2 anode at 2000 mA g−1 [30]. (F) illustration of the synthesis of single-layer MXenes and MoSe2/MXenes heterojunction [31]. (G) The SnS/Ti3C2Tx composites were synthesized by hydrothermal and annealing methods [32]. (H) The galvanostatic discharge/charge voltage profiles of the SnS/Ti3C2Tx composites at 100 mA g−1 [32]. (I) The rate capability of SnS/Ti3C2Tx electrode [32]. (J) The cycling performance of SnS/Ti3C2Tx composites with a current density of 500 mA g−1, and the corresponding coulombic efficiency [32].
Figure 3. (A) Schematic illustration of the synthetic process for VO2/MXenes hybrids [29]. (B) SEM images of the VO2/MX-1[29]. (C) Cyclic performances of VO2/MX, VO2 and MX at a current of 0.1 A g−1 [29]. (D) Schematic illustration for synthesizing the NTO/Ti3C2 composite [30]. (E) Long-term cycling performance and CE data of the NTO/Ti3C2 anode at 2000 mA g−1 [30]. (F) illustration of the synthesis of single-layer MXenes and MoSe2/MXenes heterojunction [31]. (G) The SnS/Ti3C2Tx composites were synthesized by hydrothermal and annealing methods [32]. (H) The galvanostatic discharge/charge voltage profiles of the SnS/Ti3C2Tx composites at 100 mA g−1 [32]. (I) The rate capability of SnS/Ti3C2Tx electrode [32]. (J) The cycling performance of SnS/Ti3C2Tx composites with a current density of 500 mA g−1, and the corresponding coulombic efficiency [32].
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Figure 4. (A) The design concept and synthesis process of electrode materials for SIBs with high volumetric and gravimetric capacity [38]. (B) SEM images of MX/SnS2 [38]. (C) Galvanostatic charge-discharge profiles of MX/SnS2 5:1 [38]. (D) Rate performance [38]. (E) The preparation process of the Ni0.5Co0.5Se2/Ti3C2Tx [39]. (F) Schematic illustration of synthetic process for TiO2@Ti3C2Tx material [40].
Figure 4. (A) The design concept and synthesis process of electrode materials for SIBs with high volumetric and gravimetric capacity [38]. (B) SEM images of MX/SnS2 [38]. (C) Galvanostatic charge-discharge profiles of MX/SnS2 5:1 [38]. (D) Rate performance [38]. (E) The preparation process of the Ni0.5Co0.5Se2/Ti3C2Tx [39]. (F) Schematic illustration of synthetic process for TiO2@Ti3C2Tx material [40].
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Figure 5. (A) Schematic illustration of the strategy for preparing M-SnP-in hybrids [41]. (B) Cycling performance tested at 2 A g−1 for 1500 cycles [41]. (C) Synthesis process diagram of FePS3@MXenes and Schematic illustration of MXenes assembled on FePS3 nanosheets surface and the micromolecular structure in enlarged view FePS3@MXenes [41]. (D) SEM images of FePS3@MXenes [42]. (E) Schematic diagram generalizing the preparation [42]. (F) Schematic diagram generalizing the preparation of T-MXene@C [44]. (G) Low-magnification TEM [44].
Figure 5. (A) Schematic illustration of the strategy for preparing M-SnP-in hybrids [41]. (B) Cycling performance tested at 2 A g−1 for 1500 cycles [41]. (C) Synthesis process diagram of FePS3@MXenes and Schematic illustration of MXenes assembled on FePS3 nanosheets surface and the micromolecular structure in enlarged view FePS3@MXenes [41]. (D) SEM images of FePS3@MXenes [42]. (E) Schematic diagram generalizing the preparation [42]. (F) Schematic diagram generalizing the preparation of T-MXene@C [44]. (G) Low-magnification TEM [44].
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Figure 6. (A) Schematic illustration of transitional metal chalcogenide (TMC)on MXene coated fungal-derived carbonaceous nanoribbon (CNRib) heterostructure (TMC@MXene@CNRib) [49]. (B) Cycling performances at current density of 1 A g−1 [50]. (C) SEM images of MXene@CoS2/NC spheres in sequence [51]. (D) Long-term cycling stability of MXene@CoS2/NC [52]. (E) Schematic diagram of the preparation process of a 3D-printed V2CTx/rGO-CNT microgrid aerogel electrode [52]. (F) Schematic diagram of fabrication procedure for Ti3C2Tx-CC skeletons and Na-Ti3C2Tx-CC metal anodes [53].
Figure 6. (A) Schematic illustration of transitional metal chalcogenide (TMC)on MXene coated fungal-derived carbonaceous nanoribbon (CNRib) heterostructure (TMC@MXene@CNRib) [49]. (B) Cycling performances at current density of 1 A g−1 [50]. (C) SEM images of MXene@CoS2/NC spheres in sequence [51]. (D) Long-term cycling stability of MXene@CoS2/NC [52]. (E) Schematic diagram of the preparation process of a 3D-printed V2CTx/rGO-CNT microgrid aerogel electrode [52]. (F) Schematic diagram of fabrication procedure for Ti3C2Tx-CC skeletons and Na-Ti3C2Tx-CC metal anodes [53].
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Figure 7. (A) Schematic diagram showing the crystal structure of a Ti3C2 monolayer with top and side view. The large blue balls represent Ti atoms and the small brown balls represent C atoms. The highlighted unit cell indicates the high-symmetry A, B, and C adatom [54]. (B) Schematic representation of the top view of the energetically optimized migration pathways and the corresponding diffusion barrier profiles of Na [54]. (C) Distribution of the energy barrier profiles of Na diffusion under Different interlayer spacings in C–Ti stacking of Ti3C2O2 [55]. (D) Distribution of the energy barrier profiles of Na diffusion under Different interlayer spacings in C-Ti stacking of C-Tistacking of Ti2CO2 [55].
Figure 7. (A) Schematic diagram showing the crystal structure of a Ti3C2 monolayer with top and side view. The large blue balls represent Ti atoms and the small brown balls represent C atoms. The highlighted unit cell indicates the high-symmetry A, B, and C adatom [54]. (B) Schematic representation of the top view of the energetically optimized migration pathways and the corresponding diffusion barrier profiles of Na [54]. (C) Distribution of the energy barrier profiles of Na diffusion under Different interlayer spacings in C–Ti stacking of Ti3C2O2 [55]. (D) Distribution of the energy barrier profiles of Na diffusion under Different interlayer spacings in C-Ti stacking of C-Tistacking of Ti2CO2 [55].
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Figure 8. (A) Adsorption configurations of Na2Sen (n = 8, 6, 4, 2, and 1, respectively) on the surface) and pristine Ti3C2 [57]. (B) Total and partial density of states (DOS) of N-doped Ti2C monolayer with doping concentrations of (a) 0%, (b) 6.25%, (c) 11.1%, (d) 25%, (e) 50% and (f) 100%, i.e., Ti2N monolayer. a is the lattice constant for a per unit cell at different concentrations of nitrogen [59]. (C) (a–c) the most stable adsorption configurations for another Na adsorption on top of functional groups in the heterostructures, such as -F, -O and -OH. (d) The calculated binding energies for Na adsorption on the surface of BP nanoparticle or PDDA-BP/Ti3C2 heterostructures with different surface functional groups [37]. (D) Cycle performance for Ti3C2Tx at 20 mA g−1 [61].
Figure 8. (A) Adsorption configurations of Na2Sen (n = 8, 6, 4, 2, and 1, respectively) on the surface) and pristine Ti3C2 [57]. (B) Total and partial density of states (DOS) of N-doped Ti2C monolayer with doping concentrations of (a) 0%, (b) 6.25%, (c) 11.1%, (d) 25%, (e) 50% and (f) 100%, i.e., Ti2N monolayer. a is the lattice constant for a per unit cell at different concentrations of nitrogen [59]. (C) (a–c) the most stable adsorption configurations for another Na adsorption on top of functional groups in the heterostructures, such as -F, -O and -OH. (d) The calculated binding energies for Na adsorption on the surface of BP nanoparticle or PDDA-BP/Ti3C2 heterostructures with different surface functional groups [37]. (D) Cycle performance for Ti3C2Tx at 20 mA g−1 [61].
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Su, D.; Zhang, H.; Zhang, J.; Zhao, Y. Design and Synthesis Strategy of MXenes-Based Anode Materials for Sodium-Ion Batteries and Progress of First-Principles Research. Molecules 2023, 28, 6292. https://doi.org/10.3390/molecules28176292

AMA Style

Su D, Zhang H, Zhang J, Zhao Y. Design and Synthesis Strategy of MXenes-Based Anode Materials for Sodium-Ion Batteries and Progress of First-Principles Research. Molecules. 2023; 28(17):6292. https://doi.org/10.3390/molecules28176292

Chicago/Turabian Style

Su, Dan, Hao Zhang, Jiawei Zhang, and Yingna Zhao. 2023. "Design and Synthesis Strategy of MXenes-Based Anode Materials for Sodium-Ion Batteries and Progress of First-Principles Research" Molecules 28, no. 17: 6292. https://doi.org/10.3390/molecules28176292

APA Style

Su, D., Zhang, H., Zhang, J., & Zhao, Y. (2023). Design and Synthesis Strategy of MXenes-Based Anode Materials for Sodium-Ion Batteries and Progress of First-Principles Research. Molecules, 28(17), 6292. https://doi.org/10.3390/molecules28176292

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