Skip to main content

Effect of vacancies and edges in promoting water chemisorption on titanium-based MXenes


The functionality of two-dimensional (2D) transition metal carbides and nitrides (MXenes) in technological applications greatly depends on their wettability. For instance, MXenes’ layer stability against degradative oxidation is notably reduced when stored in aqueous solutions, leading to the transformation into oxides. In this work, we study water adsorption on Ti-based MXenes by ab initio calculations. The energy gains for the molecular adsorption on Tin+1XnT2 is evaluated as a function of the termination (T = F, O, OH, mixture), the carbon/nitrogen ratio (X = C, N), the layer thickness (n) and water coverage. MXenes’ hydrophilicity tends to increase due to the presence of defects as vacancies and flake edges. We demonstrate that physical adsorption occurs through hydrogen bonding on both defect-free layers and layers containing C/N or Ti atomic vacancies, with –OH terminations providing the strongest interactions (0.40–0.65 eV). In contrast, strong water chemisorption is observed on surfaces with a single termination vacancy (0.60–1.20 eV), edges (0.75–0.85 eV), and clusters of defects (1.00–1.80 eV). We verified that the presence of undercoordinated Ti atoms on the surface is the key factor in promoting H2O chemisorption, i.e., the degradative oxidation.

Graphical Abstract

1 Introduction

Two-dimensional (2D) transition metal carbides, nitrides and carbonitrides (MXenes) are among the most studied 2D materials today owing to their wide technological applicability [1, 2]. They are conventionally described by the chemical formula Mn+1XnTx, for which M represents an early transition metal (Ti, V, Cr, Mo, Nb, etc.), X is carbon or/and nitrogen, Tx is the number (x) and type (T) of surface terminations, while n stands for the layer thickness (n = 1–4) [3,4,5]. By varying MXenes’ synthesis and composition, their physico-chemical properties can be intentionally designed. After MXenes’ first synthesis in 2011 [6], several applications have been proposed and explored, such as energy conversion and storage [7, 8], sensors [9, 10], electromagnetic interference shielding [11, 12], catalysis [13,14,15] and tribology [16, 17].

For many applications, the precise understanding of the wettability of 2D materials is mandatory to improve their functionality. It is known that the properties of 2D materials depend on environmental conditions [18, 19]. For instance, the presence of water promotes low-friction sliding between graphene layers, while it worsens the tribological performance of molybdenum disulfide (MoS2) [20, 21]. The influence of humidity on the tribological behavior has been also investigated for Ti3C2Tx multi-layer coatings by Marian et al., finding that the friction and wear performance is detrimental for higher relative humidities [22]. It is well accepted that MXenes show an intrinsic hydrophilicity, mainly attributable to the presence of hydroxyl, oxygen and fluorine terminations [3]. However, the hydrophilicity of this family of 2D materials has been scarcely investigated with both experimental and computational approaches [23,24,25]. Contact angle measurements reveal that the wettability of MXenes is not homogeneous but can vary depending on local surface features as well as the presence of contaminations [23]. Apart from these general conclusions, a complete characterization of MXenes’ hydrophilicity is lacking.

Another important issue concerning the interaction of MXenes with water relates to their degradative oxidation. This phenomenon, spontaneously occurring under ambient conditions, inevitably compromises the synthesis and subsequent applicability of MXenes [26, 27]. Many experiments and calculations have confirmed the intrinsic tendency of MXenes to transform into oxides, while light and temperature tend to accelerate this process [25, 28,29,30,31,32,33,34]. Several factors affecting the oxidation rate of MXenes have been investigated, such as layer microstructure and atmosphere/solvent composition [26]. One of the critical factors in stability of MXenes is to know which oxidant species (O2 or H2O) is mainly responsible for the degradative process. In earlier studies, oxygen dissolved in MXenes’ colloidal solutions was thought to play the major role [33]. However, recent studies on the oxidation kinetics performed by ultraviolet–visible and Raman spectroscopy revealed that water seems to be the key component leading to degradation [35]. Recently, atomistic insights on MXenes’ oxidation in aqueous solutions were provided by means of first principle molecular dynamics (MD) simulations [25]. Their results strongly support the experimental observation that water is an oxidant, which is strong enough to attack and degrade MXenes.

In this context, fundamental aspects regarding the interaction of MXenes with water need to be unraveled. The characterization of hydrophilicity for different sites, both defective and not, can be a starting point for further investigations. In this work, we exploit Density Functional Theory (DFT) calculations to study the interaction of H2O with Ti-based MXenes. We mapped the hydrophilicity of defect-free surfaces by varying the termination type (T), the carbon/nitrogen ratio (X), as well as the layer thickness (n). The analysis is repeated for defective MXene flakes, as they are known for being prone to oxidation [36,37,38]. The role of single atomic vacancies, cluster of defects, and edges in promoting the chemisorption of water is addressed and explained, focusing on both energetical and structural aspects. Since MXene surfaces are usually terminated with a random distribution of –F, –O and –OH groups [38,39,40,41], we also map the hydrophilic areas for mixed terminated MXenes. Lastly, we discuss the influence of increasing water coverage on the adsorption process.

2 Systems and methods

The analysis was performed by means of spin-polarized DFT calculations as implemented in the version 6.7 of the Quantum ESPRESSO suite [42,43,44]. We used the generalized gradient approximation (GGA) within the Perdew–Burke–Ernzerhof (PBE) parametrization to describe the exchange-correlation functional [45]. To properly consider the van der Waals interactions, we used an ad-hoc modification of the Grimme D2 dispersion correction scheme (i.e., DNG) [46, 47], which differs from the standard D2 only for the C6 coefficient and the van der Waals radius R0 of the Ti atoms, which are replaced with those of Ar, i.e. the preceding noble gas in the periodic table (hence the acronym NG). In a previous work, [46] we demonstrated that the use of PBE + DNG is more accurate in capturing long-range van der Waals interactions than other dispersion-corrected DFT functionals (e.g. vdW-DF2) when MXenes are involved. The electronic wave-function was expanded on a plane-wave basis, truncated with a cutoff of 50 Ry, while a cutoff of 400 Ry was applied for the charge density, in agreement with our previous study on Ti-based MXenes [46]. The ionic species were described by ultrasoft pseudopotentials. The structural relaxations were carried out using convergence thresholds of 10−4 Ry and 10−3 Ry/Bohr for the total energy and the atomic force components, respectively, while Gaussian smearing of 0.02 Ry was used to better describe the electronic states occupation around the Fermi level. Additional information on convergence tests is shown in Additional file 1: Fig. S1.

To model MXene surfaces, we considered 4 × 4 orthorhombic supercells, ensuring at least 15 Å of vacuum between periodic replicas along the z direction. To model MXene edges, the b lattice parameter of the supercell was doubled, leading to distances between ribbon replicas of at least 10 Å along the y direction. For all surfaces, the sampling of the Brillouin zone was done with a 3 × 4 × 1 k-points Monkhorst-Pack grid, while an equivalent reduced 3 × 2 × 1 grid was used for the ribbons [48]. To model the isolated water, we employed a cubic cell with side of about 25 Å, which is large enough to consider the molecule as isolated. More details on the supercells are provided in Additional file 1: Figs. S2, S3.

An exemplary selection of the MXene models employed is depicted in Fig. 1. First, we considered eight orthorhombic defect-free surfaces: six layers having the general formula Ti2XT2, with X = C or N, and T = F, O or OH, one thicker layer with formula Ti4C3F2, and a mixed-terminated MXene surface. For the latter case, the 4 × 4 orthorhombic model allowed us to simultaneously consider 16 surface groups, that we randomly assigned to be 6 –F, 5 –O and 5 –OH groups (Fig. 1a). Then, by removing a termination (VT), a titanium atom (VTi), or a carbon/nitrogen atom (VX), we introduced a single-atom defect, as schematically reported in Fig. 1b. We modelled a vacancy concentration of 6.25%, obtained by the removal of one atom from the employed 4 × 4 supercell. This value is compatible with data on Ti3C2Tx monolayers obtained by scanning transmission electron microscopy (STEM) measurements that suggest a large range of defect densities depending on the synthesis conditions as well as the quality of the initial bulk precursor [49, 50]. Indeed, single-atom defects are commonly found in MXenes synthesized with low etchant concentrations. Vacancy clusters are often detected for harsher synthesis conditions (e.g., high hydrofluoric acid concentrations).

Fig. 1
figure 1

a Top-view of the 4 × 4 orthorhombic cell employed for the mixed terminated MXene surface. The supercell is also representative of homogeneously terminated surfaces. b Schematic of the single atomic defects considered: termination (VT), titanium (VTi) and carbon/nitrogen (VC/N) vacancies. c Perspective view (above) and cross-section (below) of the Ti8C3O8 nanoribbon, that we used for the edge effect oxidation. In the lower right corner, we provided a schematic of the octahedral coordination usually found for Ti atoms in MXenes, which instead is distorted in nanoribbons. Chemical elements are represented by different colors: Ti-grey, C-black, F-green, O-red, H-white

We compared our models with those of Gouveia et al. [51], finding an excellent agreement in terms of vacancy formation energy and structural features. Layers with clusters of vacancies were modelled by removing at least two adjacent atoms from the surface. For instance, a “pVTi + qVT” cluster is obtained by removing p atoms of Ti and q termination groups (p = 1, 2 and q = 1, 2, 3). MXene nanoribbons were built according to the work of Zhao et al. [52], in which the stability of different edge reconstructions for Ti2CT2 (with T = F, O or OH) was investigated by means of DFT. We focused on those zigzag nanoribbons having the empirical formula Ti8C3T8 that showed the lowest edge energy. To model the analogous nitrogen-based ribbons, i.e., Ti8N3T8, we kept the same geometrical structure, allowing the relaxation of the atomic positions. In Fig. 1c, we exemplarily present a perspective and a sectional view of the Ti8C3O8 nanoribbon, with the outermost Ti atoms that have lost their typical octahedral geometry in favor of a distorted tetrahedral coordination.

The partial atomic charges were evaluated by means of the Bader Charge analysis [53,54,55,56]. The adsorption energy (Eads) is calculated as the difference between the total energy of the interacting system and the sum of the energies of the substrate and the isolated water molecule. To study the dependence of Eads on the water coverage, we normalized the energy value by the number n of adsorbed water molecules:

$${\text{E}}_{\text{ads}}\left(n\right)=\frac{{\text{E}}_{\text{total}}-(n\cdot {\text{E}}_{{\text{H}}_{2}\text{O}}+{\text{E}}_{\text{substrate}})}{n}$$

We will refer to the energy gain (Egain) as the absolute value of the adsorption energy (i.e., Egain = |Eads|).

To increase the probability of finding the lowest energy configuration for the adsorbed water, we explored different starting molecular configurations as reported in Additional file 1: Fig. S4. They differ regarding the H2O orientation relative to the surface (in-plane water, oxygen-up and oxygen-down), the H2O rotation angle with respect to the perpendicular axis and the lateral position. Despite a large number of initial configurations, the final geometries were often equivalent, coinciding with local minima or global minimum.

3 Results and discussion

We have divided our results and discussion into seven sections. The first section holistically summarizes the energetics calculated for all systems considered in this work. In the subsequent Sect. 3.23.5, the physical interpretation for the configurational aspects of the MXene–water interaction is presented for each type of surface. Finally, we present the hydrophilicity map for a mixed terminated MXene (Sect. 3.6) and the influence of the water coverage on the average adsorption energy (Sect. 3.7).

3.1 Hydrophilicity of MXenes

The hydrophilic character of a material at the atomistic level can be related to the energy gain associated with the adsorption of water molecules. Energy gains related to the adsorption of a single water molecule are displayed for the defect-free (Fig. 2a) and single vacancy-containing MXenes (Fig. 2b). We studied Ti2XT2 as the example MXene and investigated the effect of the surface termination (T = F, O and OH), carbide vs. nitride (X = C and N), and the presence of vacancy on the metal site (VTi), on the X site (VC/N) and the surface termination sites (VT). We also studied MXenes with a higher thickness (i.e., Ti4C3F2) to a limited extend, due to the increased computational effort required for simulating these larger systems. However, it is known that adsorption phenomena mainly affect the atoms closest to the surface, which agrees with our findings. Therefore, no remarkable differences were found when switching from a thinner MXene (Ti2CF2) to a thicker analogous (Ti4C3F2).

Fig. 2
figure 2

Absolute values of the adsorption energy of one single water molecule on different types of MXenes: a defect-free surfaces, b surfaces with single vacancy of C/N (VC/N), Ti (VTi) or termination (VT), c edges, d, e surfaces with cluster of defects (pVTi + qVT), consisting of p Ti vacancies and q termination vacancies. f Summarizes all cases considered. The highlighted intervals reflect the extent of the interaction with water: blue stands for strong chemisorption and green reflects physisorption, while red points to an intermediate behavior

The fully terminated surfaces interact with water via hydrogen bonds. Fluorine and oxygen terminations can act as weak H-bond acceptors, while hydroxyls can also play the role of the donor. This behavior leads to an increase in the energy gain by moving from –F and –O (0.12–0.29 eV) to –OH (0.43–0.49 eV) terminated surfaces (Fig. 2a). In any case, adsorption energies of H2O are greater on MXene monolayers compared to other 2D materials such as graphene or MoS2 (0.12–0.15 eV) [57], demonstrating their intrinsic hydrophilic behavior.

In general, the removal of an atom from a surface (i.e., single vacancy) was supposed to enhance its reactivity towards water adsorption [58]. However, for the internal MXene vacancies, including C/N vacancies (VC/N shown as red circles) and Ti vacancies (VTi, shown as blue triangles), the interaction with H2O appears to be almost the same as for the defect-free MXenes (Fig. 2b). The negligible change in energy could be explained by the fact that the water molecule is not small enough to approach these internal defects, resulting in negligible stabilization. In the case of termination vacancies (VT, as shown as green triangles), the dangling bonds of the underlying Ti atoms make the surface extremely reactive. The oxygen atom of H2O can physically fill the hole left by the missing Tx, and due to its two lone pairs, it can provide stability to the undercoordinated Ti atoms. For the Tx-vacancy, the associated energy gains range from 0.61 to 1.18 eV, depending on the reactivity of the MXene (Fig. 2b). It is worth noting that the water adsorption energy on MXene surfaces with Tx-vacancy is comparable to that of titanium dioxide (TiO2) reported in literature. The most common polymorphs of TiO2, anatase and rutile, are both composed of distorted TiO6 octahedra, with the Ti atoms showing octahedral coordination similar to MXene layers. As reported in Ref. [59], water interacts with the anatase (101) and rutile (110) crystal faces through the coordination of the water oxygen atom to the outermost Ti atoms. Indeed, the exposed Ti atoms are undercoordinated (fivefold-coordinated), thus prone to being stabilized by the oxygen atom of water. Interestingly, based on DFT calculations [60, 61], the water adsorption on the (101) crystal face of anatase and (110) face of rutile is found to be 0.84 and 0.94 eV, respectively, which is within the Eads energy range observed for MXene’ surfaces with defects.

As the next step in our analysis, we considered the effect of MXene edges as the defects. Figure 2c refers to the water interaction with MXene edges showing the lowest formation energy [52]. At the MXene edges, the outermost Ti atoms have lost their typical octahedral geometry, which become defects sites that can interact with H2O (see Sect. 3.4). Because the edges are mainly undercoordinated Ti atoms, the strength of the interaction is almost independent of the MXene composition, ranging between 0.73 and 0.85 eV (red triangles in Fig. 2c). This finding agrees with the fact that in almost all MXenes, 2D flakes’ edge oxidation can be observed during storage regardless of the flake composition and the number of transition metal layers (n) in MXene, and edge capping has been utilized as a way to slow down the oxidation [62, 63].

Finally, the energy gains concerning H2O interacting with a cluster of defects are presented in Fig. 2d, e. We explored a wide range of 2D flakes consisting of a single (or double) Ti vacancy and one, two and three termination vacancies. Generally, all energy gains are greater than 1.00 eV, suggesting the strong chemisorption of the water. Some exceptions are found for those layers functionalized with –OH with one Ti vacancy (Fig. 2d), that are not reactive enough to promote the chemisorption of water. This peculiar deviation between –OH and –F/–O terminated MXene flakes will be addressed in detail in the following sections.

Figure 2f shows a collective representation of the water adsorption energies on MXene flakes from defect-free to vacancy clusters. We divided the energy values into three regions, according to the nature and strength of the molecule-surface interaction. The green region ranging between 0.10 and 0.55 eV includes pure physisorption of water via hydrogen bonds. For Eads greater than 0.60 eV, the oxygen of water establishes chemical bond(s) with the undercoordinated Ti atom(s) of the surface, leading to chemisorption. We distinguished a weak chemisorption, 0.6 eV < Eads < 1.0 eV (red region), from a stronger chemisorption, Eads above 1.00 eV (blue region). Defect-free MXenes and single vacancies of Ti and C/N (in green) lead to adsorption energies that are mainly affected by the type of termination (T). For these surfaces, the interaction with water does not exceed 0.55 eV (green region). Intermediate energy values (0.60–0.90 eV) are mainly found for water on single termination vacancies and edges. In contrast, the energy range associated with clusters of vacancies (0.90–1.80 eV), highlighted in blue, is the highest among all and compatible with strong chemisorption of water (i.e., shorter Ti–OH2 bond distances). Figure 2f identifies defect clusters as the sites interacting more strongly with the H2O molecule irrespective of the termination type and the carbon/nitrogen content as discussed in Sect. 3.5.

3.2 Water adsorption on defect-free surfaces

The optimized adsorption configurations of water on defect-free surfaces are illustrated for Ti2CO2 and Ti2C(OH)2 in Fig. 3a, d. For these MXene surfaces, the role of layer thickness and carbon/nitrogen content are negligible compared to the effect induced by the termination. In particular, –F and –O behave similarly, acting as weak acceptors of hydrogen bonds. Due to the electrostatic repulsion between the passivating groups and the oxygen of water, only a slight approach is allowed (Fig. 3a). Therefore, long-distance H-bonds are established (the distances between H2O and –F and –O terminations are in the range 2.34–2.43 Å), resulting in weak interactions. In contrast, –OH terminations (Fig. 3d) can act as donors of hydrogen bonds, leading to shorter distances (1.97–2.03 Å) and stronger interactions.

Fig. 3
figure 3

Perspective view of the optimized configuration of H2O interacting with (a, d) defect-free MXenes, (b, e) surfaces with a vacancy of termination (VT), and (c, f) edge of ribbons. Ti2CO2 (above) and Ti2C(OH)2 (below) are taken as examples. The yellow arrow highlights the presence of the water molecule. Ti atoms are shown in gray, O in red, C in black and H in white

3.3 Water adsorption on surfaces with single-atom defects

Single vacancy sites were modeled by removing the atoms closest to the surface, in three types, VT, VTi and VC/N as a surface with a vacancy of termination, titanium, and carbon/nitrogen, respectively. In Fig. 3b, e, we shown the optimized configurations of the water molecule on Ti2CO2 and Ti2C(OH)2 surfaces with a missing termination (VT). Configurations concerning other vacancy sites (i.e., VTi and VC/N) are provided in Additional file 1: Fig. S5. Generally, the same optimized orientation of H2O was found when interacting with F- and O-terminated nitrides and carbides. This characteristic probably relates to the similar physical-chemical properties (e.g., high electronegativity, H-bonds acceptor capability) of both terminations. Moreover, OH-terminated carbides and nitrides retain a similar behavior to each other as well.

Neither VC/N nor VTi affects the interaction with water compared to defect-free surfaces. Once again, the formation of hydrogen bonds is the main driving force that regulates the interaction. However, the optimal H-bond distance was found to vary on defective surfaces and followed a specific trend. Taking Ti2NF2 as an example, the average H-bond distance is 2.37 Å, 2.33 Å and 2.20 Å for a defect-free surface, VC/N and VTi, respectively.

The reactivity towards water can be notably increased in the presence of surface termination vacancies (VT), favoring the transition from physisorption to chemisorption (green triangles in Fig. 2b). The absence of one surface termination causes undercoordination of the three surrounding Ti atoms. Some of these dangling bonds can be saturated by the lone pairs of the oxygen atom of water. However, only for surfaces terminated with –F and –O, water can approach the Ti-atoms (Fig. 3b). In contrast, for surfaces with a single OH-vacancy in Ti2N(OH)2 and Ti2C(OH)2, hydroxyl groups close to the VT defect tend to trap H2O into a H-bond network, before reaching the chemisorption site (Fig. 3e). The chemisorption values vary between 0.61 and 1.18 eV for F- and O-terminated surfaces, while the absolute values depend on various factors. We identified three main contributions to this variation: (i) the residual positive atomic charge of the undercoordinated Ti atoms, (ii) the equilibrium distance between the oxygen atom of water and titanium, (iii) the number of Ti atoms stabilized by the water chemisorption. For instance, the energy gains obtained on VT substrates for Ti2NF2 (0.61 eV), Ti2CF2 (0.91 eV) and Ti2NO2 (1.17 eV) show a correlation with the partial atomic charges of the Ti atoms surrounding the vacancy (qTi = + 1.45e, + 1.53e, + 1.65e, respectively). Although the high value of qTi found on Ti4C3F2 (+ 1.60e) and Ti2CO2 (+ 1.79e), for these two MXenes the oxygen atom of H2O was found to stabilize only one titanium, instead of two. This compensation leads to the energy fluctuation trend shown in Fig. 2b.

3.4 Chemisorption on edges

To study the effect of MXene flake edges, we focused on MXene ribbons (1D MXenes). Different reactive sites appear on the edges, depending on the specific cut and reconstruction. However, based on a study on MXene nanoribbons [49], we decided to restrict our study to those nanoribbons that have the lowest formation energy, thus showing the highest stability. Therefore, the adsorption values collected in Fig. 2c, ranging between 0.73 and 0.85 eV, can be considered as the lower limit that can easily increase in presence of more unstable edges. Representations of the optimized Ti8X3T8 nanoribbons (X = C or N, and T = F, O or OH) are presented in Additional file 1: Fig. S6. The main geometrical feature of the MXene edge (nanoribbons) is a distortion of the chemical bonds between Ti atoms and surface terminations. At the edge, the classical octahedral geometry is lost for the outermost Ti atoms, leading to an unconventional distorted tetrahedral coordination (Fig. 1c).

The configurations of water interacting with MXene edges (1D-MXenes Ti8C3O8 and Ti8C3(OH)8) are provided in Fig. 3c, f. The defective undercoordinated Ti atom along the edges constitutes the most reactive site to interact with water. Regardless of the termination type and C/N content, the oxygen of water interacts with one or two undercoordinated Ti atom(s), similarly to the MXene flake with a termination vacancy (VT). We found that the energy gain mainly depends on the H2O–Ti distance, the number of Ti atoms involved, and the H2O-assisted reconstruction of the edge. In most cases (including Fig. 3f), water interacts with a single titanium atom, with a narrow H2O–Ti distances distribution (2.25−2.31 Å). In other cases (Fig. 3c), H2O prefers to interact with two Ti atoms, leading to an increase in the average distance. A visible reconstruction of the edge is observed only for Ti8C3F8, where a –F termination moves inwards, giving way to the oxygen of water to interact with the edge (Additional file 1: Fig. S6). For other systems, only minor displacements can be seen, such as slight rotations of –OH groups.

3.5 Chemisorption on vacancy clusters

Various combinations of titanium (VTi) and termination (VT) vacancies were considered as defect clusters (pVTi + qVT), exploring p = 1, 2 and q = 1, 2, 3. In Fig. 4, we only focus on single Ti vacancy cases (p = 1) with vacancy clusters on surface terminations (q = 1, 2, 3), providing the optimized configurations for two representative materials, i.e., Ti2CF2 and Ti2C(OH)2. In Additional file 1, the configurations of water adsorbed on 2VTi + qVT clusters are also shown and discussed.

Fig. 4
figure 4

Optimized configurations of H2O adsorbed on different clusters of vacancies for Ti2CF2 (ac) and Ti2C(OH)2 (df). The clusters of defects consist of one titanium vacancy and up to three termination vacancies, as 1VTi + 1VT (a, d), 1VTi + 2VT (b, e) and 1VTi + 3VT (c, f). The yellow arrow highlights the presence of the water molecule interacting with the defected Ti2C(OH)2 surface

For vacancy clusters (1VTi + qVT) on O- and F-terminated MXenes (Fig. 4a–c), the H2O molecule provides two strong stabilizing effects. First, the oxygen atom of water saturates a VT, interacting with the remaining two surrounding Ti atoms. Moreover, one H of the water can point towards the hole left by VTi. With the lack of a titanium atom, many T and C/N atoms become undercoordinated, leading to a densification of the negative charge centered on the VTi defect. This excess of charge density is mitigated when one of the two positively charged hydrogens of H2O is pointed towards the hole. It is worth noting that the excess of charge density is reduced with an increasing number of VT. In other words, when a VTi is formed, the more neighboring terminations are missing, the less reactive the surface will be.

For OH-terminated MXenes (Fig. 4d–f), similar configurations are found, except for 1VTi + 1VT cluster. This peculiar defect (Fig. 4d) is already stabilized without the necessity of interacting with the water molecule. Due to the lack of a titanium atom, the surrounding hydroxyl terminations can rotate and point the hydrogens towards the hole. When the number of terminations surrounding the VTi is reduced (Fig. 4e, f), the configuration becomes closer to the one observed for F-and O-terminated materials.

These considerations also explain the energy value trends in Fig. 2d. All energy gains are greater than 1.00 eV, except for the 1VTi + 1VT clusters on OH-terminated surfaces, where the re-orientation of hydroxyls reduces their reactivity. Furthermore, for O- and F-terminated surfaces, the energy gains related to the water chemisorption on 1VTi + qVT clusters decrease with increasing q due to the loss of reactivity explained before. However, energy fluctuations may also result from the complex interplay between other factors. The average distance between the oxygen atom of water and Ti atoms, as well as the positive atomic charge on Ti atoms, are also found to affect the extent of the water chemisorption.

The chemisorption of water on 2VTi + qVT clusters (q = 1, 2, 3) is regulated by almost the same mechanisms discussed above, i.e., for the 1VTi + qVT clusters. The full discussion for these defective sites is provided in Additional file 1: Fig. S7, while only a few comparative comments are presented here. The main difference between 2VTi + qVT and 1VTi + qVT lies in the number of undercoordinated Ti atoms stabilized by the oxygen atom of H2O. In the case of 2VTi + qVT, indeed, the presence of a double VTi leaves only one titanium atom with dangling bonds and leads to smaller energy gains compare to 1VTi + qVT (Fig. 2e). The energy gains related to the chemisorption of water for 2VTi + qVT are still greater than 1 eV. This can be explained by the fact that even if H2O interacts with only one Ti atom, the H2O–Ti bond distance is reduced (Additional file 1: Fig. S8), becoming comparable to the typical bond distance between Ti and Tx in a defect-free layer.

3.6 Effect of mixed terminations

It is known that as synthesized MXene surfaces are generally covered by a mixture of randomly distributed surface terminations [38,39,40,41]. Our group has already verified that the chemical behavior of mixed and homogeneous MXene surfaces can be quite different from each other [46]. To gain a better understanding of MXenes oxidation, we investigated the interaction of water with a Ti2CTx layer simultaneously passivated with –F, –O and –OH (in a stoichiometric ratio of about one-third each). The hydrophilicity map of Ti2CTx (Fig. 5), was built after performing 96 separate relaxations, trying to sample all the supercell areas in a uniform way. For each optimized configuration, we collected the final position of H2O (i.e., average x and y coordinates, tiny black dots in Fig. 5), as well as the associated energy gain (blue-white scale). As a result, we created the hydrophilicity map after making the interpolation on our obtained data points. The solid curved lines in black identify level curves that connect points with the same hydrophilicity (i.e., energy gain).

Fig. 5
figure 5

Hydrophilicity map of a 2 × 2 Ti2CTx with mixed terminated surface. The two axes identify the lateral displacement on the surface, referring to the termination positions. Terminations are shown in relief on the map. Hydrophilic regions (blue) are those rich in hydroxyl groups, where hydrogen bond networks are easily formed (inset A). White regions correspond to less hydrophilic areas, where H2O interacts only moderately with the surface (inset B). Black tiny dots identify the average x and y coordinates of H2O, for each of the 96 optimized water molecules

In the hydrophilicity map presented in Fig. 5, dark blue areas highlight strongly hydrophilic areas, while white areas identify those regions that only mildly interact with water. Terminations are superimposed on the map to better appreciate their different contribution to making a surface hydrophilic. In insets A and B, we provide two exemplary configurations, corresponding to an energy gain of 0.80 eV and 0.25 eV, respectively. The unique ability of hydroxyl groups to act as H-bond donors leads to adsorption energy gains, which are always greater than 0.50 eV. Indeed, a higher density of –OH terminations leads to more interaction with water and greater hydrophilicity. In contrast, –O and –F terminations always behave as H-bond acceptors, while oxygen is always preferred whenever possible.

These results can be compared to the case of homogeneously terminated surfaces, for which the maximum adsorption energy gain was found to be ≈ 0.50 eV for Ti2C(OH)2 and Ti2N(OH)2. Consequently, the consideration of a realistic surface having a mixture of surface terminations groups makes the system even more hydrophilic. Interestingly, the tendency to strongly interact with water is not maximized for a full coverage of hydroxyl groups. A balanced ratio between hydrogen bond donors and acceptors is the key factor in inducing cooperative hydrophilic effects. Although we limited this section to defect-free mixed terminated surfaces, we suppose that an increase in the interaction with water could arise for defective surfaces, which will be addressed in a follow-up study.

3.7 Effect of water coverage

In this section, we discuss the effect of an increased water coverage from 6 to 100% for defect-free surfaces. Energy gains per water molecule are indicated with black squares in Fig. 6 for two types of Ti2CTx, namely Ti2CO2 and Ti2C(OH)2. The other MXene compositions that we studied here, Ti2CF2, Ti4C3F2 Ti2NF2, and Ti2C(OH)2 are similar to the two examples shown here (Ti2CO2 and Ti2C(OH)2) as presented in Additional file 1: Fig. S9. We decided to split the total energy gain per water molecule into two additive contributions: one arising from the interaction exclusively between H2O molecules (light blue spheres), and the other that considers the pure interaction of the water layer with the surface (red and blue triangles).

Fig. 6
figure 6

Energy gain per molecule as a function of the water coverage for a Ti2CO2 and b Ti2C(OH)2. Two contributions to the total energy (black line) are considered. The interaction between water molecules is in light blue. The interaction between the water layer and the substrate is colored depending on the type of termination. The dashed line indicates the interaction value for a single water molecule, corresponding to a coverage of 6%. Solid lines between points are guides to the eye

Regardless of the surface composition, the total energy gain (black squares) increases until it reaches a maximum value at ~ 62.5% coverage. This trend arises from the sum of the two separate contributions mentioned before. The interaction of the water layer with the surface, triangles in Fig. 6, tends to decrease while increasing the H2O coverage. At the same time, increasing the water coverage also produces a growth in the interaction between H2O molecules within the water layer (light blue dots), that reaches an asymptotic value of about 0.38 eV. This value can be traced back to the interaction energy resulting from a strong H-bonds network, which does not depend on the type of termination. Comparing the total energy gain in Fig. 6a with Fig. 6b once again suggests the higher hydrophilicity induced by –OH compared to –O groups (and –F groups in Additional file 1: Fig. S9). The ability of hydroxyl groups to act as H-bond donors is the key factor, which is reflected in increased interaction between the surface and water layer.

Ti2NO2 surface was excluded from the previous discussion as it undergoes a structural degradation, which holds true for even low water coverages. The mechanism, observed during the relaxation of the system, is depicted in Fig. 7a for a water layer composed of two molecules. The first step involves breaking the bonds between nitrogen and a Ti atom, which is extracted from the Ti atom typical reticular position to interact with the oxygen of H2O. At the same time, a proton is transferred from one molecule to another, and then to the MXene surface. The presence of a second water molecule is mandatory as it catalyzes the proton transfer from the first water to an oxygen atom of the surface termination. Furthermore, between the considered terminations, oxygen is the only surface group able to accept a proton.

Fig. 7
figure 7

Relevant steps for the Ti2NO2 degradation caused by the presence of water (a). Schematic explaining how the pPES calculations where performed and energy barriers related to the extraction of a Ti atom (b)

To investigate the unusual behavior of Ti2NO2, we computed the energetic barriers for the extraction of a titanium atom. The perpendicular Potential Energy Surfaces (pPESes) for this process are shown in Fig. 7b for 6 different layers of Ti2XT2, with X = C or N, and T = F, O or OH. pPESes are obtained by changing the z coordinate of a Ti atom and recording the energy of each configuration. Interestingly, the energy barrier related to the removal of a Ti atom has the lowest value for Ti2NO2 (0.16 eV). The intrinsic weakness of the N–Ti bonds in Ti2NO2 could explain the experimental evidence that nitride MXenes are difficult to synthesize by means of conventional etching in aqueous acidic solutions [64, 65].

Under ambient conditions, the H2O concentration is higher than the coverages considered in this study and multilayer structures are present. However, due to the lack of previous studies in literature, we consider worth starting to build some knowledge on molecular adsorption, in particular on the role of defects in strengthening the water-MXene interaction. The formation of multi-layer water structures may be promoted by the first chemisorbed molecules through the formation of hydrogen-bonds. Moreover, MXenes attract a lot of interest as solid lubricants [22]. Since the tribological properties of 2D materials, such as graphene and MoS2, are notably affected by the physical/chemical interaction of the layers with water molecules [66,67,68], we believe that the present study is useful to interpret the tribological behavior of MXenes measured for different relative humidities.

4 Conclusions

In this work, the interaction of titanium-based MXenes with water has been characterized through static DFT calculations. The intrinsic hydrophilicity of defect-free surfaces has been explored depending on the type of termination, carbon/nitrogen in X, and MXene layer thickness (n). Subsequently, we have unraveled the role of single atomic vacancies, cluster vacancies and stable edges in promoting the chemisorption of water. Our results suggest that H2O chemisorption on MXene surfaces only occurs in the presence of undercoordinated titanium atoms. The absence of at least one termination group (VT) resulted in a destabilization of the adjacent Ti atoms, which strongly interacted with the oxygen atom of water to saturate their dangling bonds. Without this dangling bond, water simply physically adsorbs on the substrate via the formation of hydrogen bonds with the terminations, i.e., –OH, –O and –F.

Physical adsorption occurs both on defect-free surfaces and substrates with a single vacancy of C/N (VC/N) or Ti atom (VTi). In these cases, energy gains are influenced by two factors: the number of established H-bonds, as well as their intensity. MXenes’ surface terminations were found to be the main regulator of these parameters compared to their layer thickness and C/N substitution. Hydroxyl groups provide the strongest interaction leading to increased adsorption values (0.40–0.65 eV) due to their unique ability to act as donors of H-bonds. In contrast, fluorine and oxygen terminations can only behave as weak H-bonds acceptors, showing long bond distances. For MXenes with –O and –F terminations, the resulting in-plane interaction with H2O (0.10–0.30 eV) is comparable to the one observed for graphene and MoS2 (0.12 eV and 0.15 eV, respectively).

Moreover, we demonstrated that an increased H2O coverage is responsible for a reduced interaction of the water layer with the surface, as well as a growth of the interaction between H2O molecules within the water layer. Regardless of the surface composition, the adsorption of an additional water molecule is thermodynamically always favored.

Water chemisorption has been observed on surfaces with a single termination vacancy (VT), on edges, and especially on almost all defect clusters (pVTi + qVT, with p = 1, 2 and q = 1, 2, 3). Whenever an unsaturated titanium atom appeared on the surface, the oxygen atom of water approached the defect and chemisorbed onto it. The energy gains are higher for the chemisorption on vacancy clusters (1.00–1.80 eV) compared to edges (0.75–0.85 eV) and termination vacancies (0.60–1.20 eV). This difference relates to an additional stabilizing effect that H2O can provide to surfaces when at least one Ti and T atom do simultaneously miss. The lack of a titanium atom accumulates the electronic charge around the VTi defect that is mitigated when one hydrogen of H2O is pointed towards the hole.

Further, our results show Ti2NO2 MXene has a structural instability in presence of water, which is associated with the extraction of a Ti atom from the surface. This result clearly supports the experimental difficulties encountered in the synthesis of Ti2NTx when conventional methods are employed.

Overall, this work suggests that defects on the MXene surfaces can promote the chemisorption of water, which is the first step towards degradative oxidation. However, high energy gains suggest that defect clusters promote chemisorption more than edges. Our results unravel the primary mechanisms responsible for MXenes’ oxidative degradation in aqueous environments and their experimentally observed hydrophilicity. Moreover, they pave the way for further investigations concerning the effects of humidity, water coverage, and intercalated water on the tribological performance of MXenes.

Availability of data and materials

The data-sets generated and/or analyzed during the current study are available in the Tribchem website, at the link (


  1. B.C. Wyatt, A. Rosenkranz, B. Anasori, 2D MXenes: tunable mechanical and tribological properties. Adv. Mater. 2007973, 1–15 (2021)

    Google Scholar 

  2. M. Alhabeb et al., Guidelines for synthesis and processing of two-dimensional titanium carbide (Ti3C2Tx MXene). Chem. Mater. 29, 7633–7644 (2017)

    Article  CAS  Google Scholar 

  3. Y. Gogotsi, B. Anasori, The rise of MXenes. ACS Nano 13, 8491–8494 (2019)

    Article  CAS  Google Scholar 

  4. G. Deysher et al., Synthesis of Mo4VAlC4 MAX phase and two-dimensional Mo4VC4 MXene with five atomic layers of transition metals. ACS Nano 14, 204–217 (2020)

    Article  CAS  Google Scholar 

  5. X. Xiao, H. Wang, P. Urbankowski, Y. Gogotsi, Topochemical synthesis of 2D materials. Chem. Soc. Rev. 47, 8744–8765 (2018)

    Article  CAS  Google Scholar 

  6. M. Naguib et al., Two-dimensional nanocrystals produced by exfoliation of Ti3AlC2. Adv. Mater. 23, 4248–4253 (2011)

    Article  CAS  Google Scholar 

  7. J. Pang et al., Applications of 2D MXenes in energy conversion and storage systems. Chem. Soc. Rev. 48, 72–133 (2019)

    Article  CAS  Google Scholar 

  8. B. Anasori, M.R. Lukatskaya, Y. Gogotsi, 2D metal carbides and nitrides (MXenes) for energy storage. Nat. Rev. Mater. 2, 1–17 (2017)

    Article  Google Scholar 

  9. S.J. Kim et al., Metallic Ti3C2Tx MXene gas sensors with ultrahigh signal-to-noise ratio. ACS Nano 12, 986–993 (2018)

    Article  CAS  Google Scholar 

  10. T. Yu, C.B. Breslin, Review—two-dimensional titanium carbide MXenes and their emerging applications as electrochemical sensors. J. Electrochem. Soc. 167, 037514 (2020)

    Article  CAS  Google Scholar 

  11. M. Han et al., Beyond Ti3C2Tx: MXenes for electromagnetic interference shielding. ACS Nano 14, 5008–5016 (2020)

    Article  CAS  Google Scholar 

  12. T. Yun et al., Electromagnetic shielding of monolayer MXene assemblies. Adv. Mater. 32, 1906769 (2020)

    Article  CAS  Google Scholar 

  13. N. Sharma, H. Ojha, A. Bharadwaj, D.P. Pathak, R.K. Sharma, Preparation and catalytic applications of nanomaterials: a review. RSC Adv. 5, 53381–53403 (2015)

    Article  CAS  Google Scholar 

  14. A. Liu et al., Recent progress in MXene-based materials: potential high-performance electrocatalysts. Adv. Funct. Mater. 30, 1–22 (2020)

    Google Scholar 

  15. Á. Morales-Garciá, F. Calle-Vallejo, F. Illas, MXenes: new horizons in catalysis. ACS Catal. 10, 13487–13503 (2020)

    Article  Google Scholar 

  16. M. Marian et al., Ti3C2Tx solid lubricant coatings in rolling bearings with remarkable performance beyond state-of-the-art materials. Appl. Mater. Today 25, 101202 (2021)

    Article  Google Scholar 

  17. P.G. Grützmacher et al., Superior wear-resistance of Ti3C2Tx multilayer coatings. ACS Nano 15, 8216–8224 (2021)

    Article  Google Scholar 

  18. C. Donnet, J.M. Martin, T. Le Mogne, M. Belin, The origin of super-low friction coefficient of MoS2 coatings in various environments. Tribol. Ser. 27, 277–284 (1994)

    Article  CAS  Google Scholar 

  19. G. Zilibotti, S. Corni, M.C. Righi, Load-induced confinement activates diamond lubrication by water. Phys. Rev. Lett. 111, 1–5 (2013)

    Article  Google Scholar 

  20. T.W. Scharf, S.V. Prasad, Solid lubricants: a review. J. Mater. Sci. 48, 511–531 (2013)

    Article  CAS  Google Scholar 

  21. J.K.G. Panitz, L.E. Pope, J.E. Lyons, D.J. Staley, Tribological properties of MoS2 coatings in vacuum, low relative humidity and high relative humidity environments. J. Vac. Sci. Technol. A 6, 1166 (1988)

    Article  CAS  Google Scholar 

  22. M. Marian et al., Effective usage of 2D MXene nanosheets as solid lubricant—influence of contact pressure and relative humidity. Appl. Surf. Sci. 531, 147311 (2020)

    Article  CAS  Google Scholar 

  23. H. Zhou et al., Study on contact angles and surface energy of MXene films. RSC Adv. 11, 5512–5520 (2021)

    Article  CAS  Google Scholar 

  24. J. Shen et al., 2D MXene nanofilms with tunable gas transport channels. Adv. Funct. Mater. 28, 1–13 (2018)

    Article  Google Scholar 

  25. T. Wu, P.R.C. Kent, Y. Gogotsi, D.E. Jiang, How water attacks MXene. Chem. Mater. 34, 4975–4982 (2022)

    Article  CAS  Google Scholar 

  26. F. Cao et al., Recent advances in oxidation stable chemistry of 2D MXenes. Adv. Mater. 34, 2107554 (2022)

    Article  CAS  Google Scholar 

  27. X. Li, Z. Huang, C. Zhi, Environmental stability of MXenes as energy storage materials. Front. Mater. 6, 2–10 (2019)

    Article  Google Scholar 

  28. R. Lotfi, M. Naguib, D.E. Yilmaz, J. Nanda, A.C.T. Van Duin, A comparative study on the oxidation of two-dimensional Ti3C2 MXene structures in different environments. J. Mater. Chem. A 6, 12733–12743 (2018)

    Article  CAS  Google Scholar 

  29. X. Li et al., A controllable heterogeneous structure and electromagnetic wave absorption properties of Ti2CT: X MXene. J. Mater. Chem. C 5, 7621–7628 (2017)

    Article  CAS  Google Scholar 

  30. A. Lipatov et al., Effect of synthesis on quality, electronic properties and environmental stability of individual monolayer Ti3C2 MXene flakes. Adv. Electron. Mater. 2, 1600255 (2016)

    Article  Google Scholar 

  31. J. Halim et al., X-ray photoelectron spectroscopy of select multi-layered transition metal carbides (MXenes). Appl. Surf. Sci. 362, 406–417 (2016)

    Article  CAS  Google Scholar 

  32. T. Habib et al., Oxidation stability of Ti3C2Tx MXene nanosheets in solvents and composite films. Npj 2D Mater. Appl. 3, 8 (2019)

    Article  Google Scholar 

  33. C.J. Zhang et al., Oxidation stability of colloidal two-dimensional titanium carbides (MXenes). Chem. Mater. 29, 4848–4856 (2017)

    Article  CAS  Google Scholar 

  34. J. Palisaitis, I. Persson, J. Halim, J. Rosen, P.O.Å. Persson, On the structural stability of MXene and the role of transition metal adatoms. Nanoscale 10, 10850–10855 (2018)

    Article  CAS  Google Scholar 

  35. S. Huang, V.N. Mochalin, Hydrolysis of 2D transition-metal carbides (MXenes) in colloidal solutions. Inorg. Chem. 58, 1958–1966 (2019)

    Article  CAS  Google Scholar 

  36. F. Xia et al., Ambient oxidation of Ti3C2 MXene initialized by atomic defects. Nanoscale 11, 23330–23337 (2019)

    Article  CAS  Google Scholar 

  37. A. Feng et al., Fabrication and thermal stability of NH4HF2-etched Ti3C2 MXene. Ceram. Int. 43, 6322–6328 (2017)

    Article  CAS  Google Scholar 

  38. M. Seredych et al., High-temperature behavior and surface chemistry of carbide MXenes studied by thermal analysis. Chem. Mater. 31, 3324–3332 (2019)

    Article  CAS  Google Scholar 

  39. M.A. Hope et al., NMR reveals the surface functionalisation of Ti3C2 MXene. Phys. Chem. Chem. Phys. 18, 5099–5102 (2016)

    Article  CAS  Google Scholar 

  40. I. Persson et al., On the organization and thermal behavior of functional groups on Ti3C2 MXene surfaces in vacuum. 2D Mater. 5, 015002 (2017)

    Article  Google Scholar 

  41. K.J. Harris, M. Bugnet, M. Naguib, M.W. Barsoum, G.R. Goward, Direct measurement of surface termination groups and their connectivity in the 2D MXene V2CTx using NMR spectroscopy. J. Phys. Chem. C 119, 13713–13720 (2015)

    Article  CAS  Google Scholar 

  42. P. Giannozzi et al., QUANTUM ESPRESSO: a modular and open-source software project for quantum simulations of materials. J. Phys. Condens. Matter 21, 395502 (2009)

    Article  Google Scholar 

  43. P. Giannozzi et al., Quantum ESPRESSO toward the exascale. J. Chem. Phys. 152, 154105 (2020)

    Article  CAS  Google Scholar 

  44. P. Giannozzi et al., Advanced capabilities for materials modelling with Quantum ESPRESSO. J. Phys. Condens. Matter 29, 465901 (2017)

    Article  CAS  Google Scholar 

  45. J.P. Perdew, K. Burke, M. Ernzerhof, Generalized gradient approximation made simple. Phys. Rev. Lett. 77, 3865–3868 (1996)

    Article  CAS  Google Scholar 

  46. E. Marquis, M. Cutini, B. Anasori, A. Rosenkranz, M.C. Righi, Nanoscale MXene interlayer and substrate adhesion for lubrication: a density functional theory study. ACS Appl. Nano Mater. 5, 10516–10527 (2022)

    Article  CAS  Google Scholar 

  47. S. Grimme, Semiempirical GGA-type density functional constructed with a long-range dispersion correction. J. Comput. Chem. 27, 1787–1799 (2006)

    Article  CAS  Google Scholar 

  48. H.J. Monkhorst, J.D. Pack, Special points for Brillouin-zone integrations. Phys. Rev. B 13, 5188 (1976)

    Article  Google Scholar 

  49. X. Sang, Y. Xie, M.W. Lin, M. Alhabeb, K.L. Van Aken, Y. Gogotsi, P.R.C. Kent, K. Xiao, R.R. Unocic, Atomic defects in monolayer titanium carbide (Ti3C2Tx) MXene. ACS Nano 10, 9193–9200 (2016)

    Article  CAS  Google Scholar 

  50. L.H. Karlsson, J. Birch, J. Halim, M.W. Barsoum, P.O.Å. Persson, Atomically resolved structural and chemical investigation of single MXene sheets. Nano Lett. 15, 4955–4960 (2015)

    Article  CAS  Google Scholar 

  51. J.D. Gouveia, J.R.B. Gomes, Structural and energetic properties of vacancy defects in MXene surfaces. Phys. Rev. Mater. 6, 1–15 (2022)

    Google Scholar 

  52. S. Zhao, W. Kang, J. Xue, MXene nanoribbons. J. Mater. Chem. C 2, 879–888 (2015)

    Article  Google Scholar 

  53. M. Yu, D.R. Trinkle, Accurate and efficient algorithm for Bader charge integration. J. Chem. Phys. 134, 1–8 (2011)

    Article  Google Scholar 

  54. G. Henkelman, A. Arnaldsson, H. Jónsson, A fast and robust algorithm for Bader decomposition of charge density. Comput. Mater. Sci. 36, 354–360 (2006)

    Article  Google Scholar 

  55. W. Tang, E. Sanville, G. Henkelman, A grid-based Bader analysis algorithm without lattice bias. J. Phys. Condens. Matter 21, 084204 (2009)

    Article  CAS  Google Scholar 

  56. E. Sanville, S.D. Kenny, R. Smith, G. Henkelman, Improved grid-based algorithm for Bader charge allocation. J. Comput. Chem. 28, 899–908 (2007)

    Article  CAS  Google Scholar 

  57. G. Levita, P. Restuccia, M.C. Righi, Graphene and MoS2 interacting with water: a comparison by ab initio calculations. Carbon 107, 878–884 (2016)

    Article  CAS  Google Scholar 

  58. S. Ferrer, J.M. Rojo, M. Salmerón, G.A. Somorjai, The role of surface irregularities (steps, kinks) and point defects on the chemical reactivity of solid surfaces. Philos. Mag. A Phys. Condens. Matter Struct. Defects Mech. Prop. 45, 261–269 (1982)

    CAS  Google Scholar 

  59. K. Bourikas, C. Kordulis, A. Lycourghiotis, Titanium dioxide (anatase and rutile): surface chemistry, liquid-solid interface chemistry, and scientific synthesis of supported catalysts. Chem. Rev. 114, 9754–9823 (2014)

    Article  CAS  Google Scholar 

  60. K. Hamraoui, S. Cristol, E. Payen, J.F. Paul, Computational investigation of TiO2-supported isolated oxomolybdenum species. J. Phys. Chem. C 111, 3963–3972 (2007)

    Article  CAS  Google Scholar 

  61. K.K. Ghuman, Mechanistic insights into water adsorption and dissociation on amorphous-based catalysts. Sci. Technol. Adv. Mater. 19, 44–52 (2018)

    Article  CAS  Google Scholar 

  62. S. Doo et al., Mechanism and kinetics of oxidation reaction of aqueous Ti3C2Tx suspensions at different pHs and temperatures. ACS Appl. Mater. Interfaces 13, 22855–22865 (2021)

    Article  CAS  Google Scholar 

  63. V. Natu et al., Edge capping of 2D-MXene sheets with polyanionic salts to mitigate oxidation in aqueous colloidal suspensions. Angew. Chem. 131, 12785–12790 (2019)

    Article  Google Scholar 

  64. B. Soundiraraju, B.K. George, Two-dimensional titanium nitride (Ti2N) MXene: synthesis, characterization, and potential application as surface-enhanced Raman scattering substrate. ACS Nano 11, 8892–8900 (2017)

    Article  CAS  Google Scholar 

  65. P. Urbankowski et al., Synthesis of two-dimensional titanium nitride Ti4N3 (MXene). Nanoscale 8, 11385–11391 (2016)

    Article  CAS  Google Scholar 

  66. M. Stella, C.D. Lorenz, M. Clelia Righi, Effects of intercalated water on the lubricity of sliding layers under load: a theoretical investigation on MoS2. 2D Mater. 8, 035052 (2021)

    Article  CAS  Google Scholar 

  67. G. Levita, M.C. Righi, Effects of water intercalation and tribochemistry on MoS2 lubricity: an ab initio molecular dynamics investigation. ChemPhysChem 18, 1475–1480 (2017)

    Article  CAS  Google Scholar 

  68. P. Restuccia, M. Ferrario, M.C. Righi, Monitoring water and oxygen splitting at graphene edges and folds: insights into the lubricity of graphitic materials. Carbon 156, 93–103 (2020)

    Article  CAS  Google Scholar 

Download references


These results are part of the SLIDE project that has received funding from the European Research Council (ERC) under the European Union’s Horizon 2020 research and innovation program. (Grant Agreement No. 865633). A. Rosenkranz gratefully acknowledges the financial support given by ANID (Chile) in the framework of the Fondecyt projects 1220331 and EQM190057.


ERC-SLIDE project (Grant Agreement No. 865633). Fondecyt projects (1220331 and EQM190057).

Author information

Authors and Affiliations



EM: investigation; formal analysis; writing—original draft. FB: investigation; formal analysis; writing—review editing. BA: formal analysis; writing—review editing. AR: formal analysis; writing—review editing. MCR: formal analysis; supervision; writing—review editing; funding acquisition. All authors read and approved the final manuscript.

Corresponding author

Correspondence to Maria Clelia Righi.

Ethics declarations

Competing interests

The authors declare that they have no competing interests.

Additional information

Publisher’s Note

Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Supplementary Information

Additional file 1.

Supercells employed in DFT calculations; strategies for the sampling of water configurations; optimized structures of MXene surfaces; structural configurations of water interacting with all the surfaces; charge analysis; correlation between adsorption energy and H2O–Ti distances; dependance of the energy gain on the water coverage for all the MXene compositions.

Rights and permissions

Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if changes were made. The images or other third party material in this article are included in the article's Creative Commons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article's Creative Commons licence and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this licence, visit

Reprints and permissions

About this article

Check for updates. Verify currency and authenticity via CrossMark

Cite this article

Marquis, E., Benini, F., Anasori, B. et al. Effect of vacancies and edges in promoting water chemisorption on titanium-based MXenes. Nano Convergence 10, 16 (2023).

Download citation

  • Received:

  • Accepted:

  • Published:

  • DOI: