# Enhancing N(2)Fixation Activity by Converting Ti(3)C(2)MXenes Nanosheets to Nanoribbons

H. Wei, Q. Jiang, C. Ampelli, S. Chen, S. Perathoner, Y. Liu, G. Centi

► To cite this version:

H. Wei, Q. Jiang, C. Ampelli, S. Chen, S. Perathoner, et al., Enhancing N(2)Fixation Activity by Converting Ti(3)C(2)MXenes Nanosheets to Nanoribbons. ChemSusChem, 2020, 13 (21), pp.5614-5619. 10.1002/cssc.202001719. hal-03216810

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# Enhanced N₂ fixation activity by converting Ti₃C₂ MXenes nanosheets to nanoribbons

Hua Wei [a, c], #, Qian Jiang [b], #, Claudio Ampelli [a], Shiming Chen [b], Siglinda Perathoner [a], Yuefeng Liu [b],* and Gabriele Centi [a],*

[a] Dr. H. Wei,<sup>#</sup> Prof. C. Ampelli, Prof. S. Perathoner, Prof. G. Centi
Dept.s ChimBioFarAm and MIFT,
V.le F. Stagno D'Alcontres 31,
98166 Messina, Italy.
E-mail: centi@unime.it

[b] Dr. Q. Jiang,<sup>#</sup> Dr. S. Chen, Prof. Y. Liu
Dalian National Laboratory for Clean Energy, Dalian Institute of Chemical Physics, Chinese Academy of Sciences,
457 Zhongshan Road, Dalian 116023, China.
E-mail: yuefeng.liu@dicp.ac.cn

[c] Dr. H. Wei
University of Lyon, Institut de Chimie de Lyon, UMR 5265 - CNRS - Université Lyon 1,
ESCPE Lyon, Laboratoire de Chimie, Catalyse, Polymères et Procédés (C2P2),
Equipe Chimie Organométallique de Surface, Villeurbanne, France

[#] These authors contributed equally to this work.

Supporting information for this article is given via a link at the end of the document.

**Abstract:** Metal carbides M₂C (MXenes) with two-dimensional (2D) structure have been indicated as promising materials for N₂ fixation, with the activity related to edge planes. We demonstrate instead here that the transformation from a 2D (nanosheets) to a 3D-type nanostructure (nanoribbons), leads to a significant enhancement of the N₂ fixation activity, due to the formation of exposed Ti-OH sites. A linear relationship is observed between ammonia formation rate and amount of oxygen on the surface of Ti₃C₂ MXene.

MXenes are metal carbide or nitride materials with a two-dimensional (2D) structure, which attracted a large interest recently for a broad range of applications such as materials for energy and environmental applications,<sup>1-4</sup> and catalysis.<sup>5-7</sup> In the latter area, several papers deal on N₂ fixation (NRR),<sup>8-18</sup> a topic of current large interest to directly produce ammonia from nitrogen.<sup>19</sup> MXene presents the unusual electronic property of the 2D structure and also the unique property of transition metal carbides, such as metallic conductivity, and the hydrophilic nature of their hydroxyl or oxygen terminated surfaces. For these properties there is a large interest on the use of MXenes as novel NRR electrocatalysts, as emerges also from the state-of-the-art comparison of NRR electrocatalysts (see Table S2). They have properties well comparable with those of the best reported NRR electrocatalysts, with the advantage of a flexible way to tune further their properties, and thus a large potential for further improvement.

Most of studies on MXenes as NRR materials indicated the need to have a 2D nanostructure, with the activity in N₂ fixation attributed generally to edge sites of the nanosheets. Luo et al.,<sup>16</sup> for example, indicate the middle Ti at the edge sites as the active sites for NRR. The mechanism proposed involved hydrogenation of undissociated N₂ molecules. Gouveia et al.<sup>6</sup> considered instead that N₂ dissociation occurs easily on the MXene (0001) surface. The top site above the metal ions on the surface of MXene nanosheets was also indicated by Wang et al.<sup>8</sup> as the sites for end-on adsorption of N₂ which is then hydrogenated, rather than

dissociated. Johnson et al.<sup>15</sup> indicated that edge sites of MXene are involved in NRR reaction and that F functional groups enhance the NRR performance in comparison to O functional groups. Xia et al.,<sup>11</sup> on the contrary, indicated that exposed Ti sites in Ti₃C₂OH facilitate the electron transfer and promote the adsorption and activation of dinitrogen. Guo et al.<sup>12</sup> suggested that OH terminal groups of MXene are inactive, indicating thus that a modification of the surface chemical states by introducing Fe heteroatoms is necessary to increase the activity.

Most of the studies based their conclusions mainly on theoretical modelling. However, notwithstanding the discordances in the nature of the active MXene materials for NRR reaction, a common agreement is that a 2D configuration is needed.

2D-type materials are an area of intense research interest for a number of applications in the field of materials for energy, including catalysis.<sup>20</sup> On the other hand, it is possible to assemble and master 2D materials to form other type of 3D-like nanomaterials.<sup>21</sup> MXenes nanosheets can be subjected to a transformation from a 2D to a 3D-like nanostructures.<sup>22</sup> This will allow to clarify the relationship between performances and type of nanostructure. In the specific case of NRR, this method of manipulating nanostructures allows to understand the role and relevance of the presence of a 2D nanostructure on edge or planar bases, by comparing the behaviour of very analogous materials, but having a different nanoshape.

We have thus investigated how the conversion of Ti₃C₂ nanosheets to 3D-like nanoribbons influence the properties and NRR reactivity to obtain insights about the role of the nanostructure in this reaction providing therefore elements for theoretical modelling to overcome the present discordances on the nature of the active materials and thus allow their better design.

Ti₃C₂ MXene nanosheets (MNSs) were prepared by HF etching (in 40% HF solution for 72h) of Ti₃AlC₂ starting precursor, followed by centrifugation, washing and drying at 60°C. The obtained MNSs are then treated in 6 M KOH for 72h (sealed container under Ar atmosphere), followed by steps as above.
<figure><img src="image_2.png" /><figcaption>**Figure 1** (a) SEM images of Ti₃C₂ MNSs (b) Top-view TEM images and electron diffraction patterns of Ti₃C₂ MNSs. (c) Cross-sectional TEM images of Ti₃C₂ MNSs. (d) SEM images of Ti₃C₂ MNRs. (e) TEM images of Ti₃C₂ MNRs and electron diffraction patterns of Ti₃C₂ MNRs. (f) HRTEM images of Ti₃C₂ MNRs, a single MNR with a width of ~ 16 nm, taken from the A position.</figcaption></figure>

Ti₃C₂ MXene nanoribbons (MNRs) are obtained in this way. The method of preparation is analogous to that used by Lian et al.²³ MNSs and MNRs were dispersed in ethanol containing 10% Nafion (ultrasonic mixing for 90 min), obtaining a homogenous ink which is then deposited by spray drying onto a gas-diffusion layer (GDL). The GDL with the deposited electrocatalyst is then hot pressed to a Nafion membrane. The electrocatalyst is located at the interface between the Nafion membrane and the GDL. The loading of the electrocatalyst resulted 0.2 mg/cm².

The electrodes were tested in an electrocatalytic flow reactor, where the hemi-cell for NRR reaction operates without a liquid electrolyte. This type of electrocatalytic reactor is different from the conventional electrocatalytic reactors operating with the electrodes immersed in a liquid electrolyte. The reason is to avoid issues related to low N₂ solubility in the electrolyte, and to allow an easier recovery of the ammonia produced. In fact, NH₃ is recovered directly from the gas outlet of the flow reactor. Details on the preparation of the electrodes, although by using different type of electrocatalysts, and on the characteristics of the electrocatalytic reactor were reported earlier.²⁴⁻²⁶ Figure S1 and related description reports also details about the flow electrocatalytic reactor, the experimental procedure of testing, the determination of ammonia and other possible products, and the series of control experiments made to verify that ammonia derives effectively from the electrocatalytic reduction of N₂.

The scanning electron microscopy (SEM) images (Figure 1a) for Ti₃C₂Tₓ (where T= F, OH) after the HF etching, show a MXene loosely layered 2D structure, indicating the successful exfoliation of Al from the MAX phase (Ti₃C₂Al). The transparency of the nanosheet presented in Figure 1b suggests that the likely presence of single layer sheet.²⁷ It presents a monocrystal as shown by diffraction pots of the selected area electron diffraction (SAED) reported in the inset of Figure 1b. The HRTEM image (Figure 1c) shows the interlayer spacing of 1.00 nm

corresponding to the (002) plane,²⁸ which is consistent with the value measured by XRD and with results obtained by Ghidiu et al.²⁹ After Ti₃C₂ nanosheets treatment by KOH, nanoribbons could be well evidenced (Figure 1d). The nanoribbons have a diameter around 16 nm, in agreement also with HRTEM images (Figures 1e and 1f).

<figure><img src="image_3.png" /><figcaption>**Figure 2** Structural characterization of Ti₃C₂ MNRs, Ti₃C₂ MNSs, and pristine Ti₃AlC₂. (a)XRD patterns of Ti₃C₂ MNRs, Ti₃C₂ MNSs, and pristine Ti₃AlC₂. (b-d) XPS spectra of Ti₃C₂ MNRs and Ti₃C₂ MNSs in the (b) C 1s, (c) O1s (d) Ti 2p, regions</figcaption></figure>

The conversion of Ti₃AlC₂ (MAX phase) to Ti₃C₂ MNSs and MNRs is confirmed by X-ray diffraction (XRD) (Figure 2a). Compared with the pattern of Ti₃AlC₂, the most intense peak (104) of Ti₃AlC₂ disappears and the (002) reflection of MXene shifts from 9.7° to
9.1° broadening at the same time. This is consistent with the expected interlayer spacing expansion in passing from Ti₃AlC₂ to Ti₃C₂ MNSs.³⁰ When the Ti₃C₂ MNSs is further treated in KOH solution, the (002) reflection shifts to 7.1° and further broaden, consistently with the further expansion of interlayer spacing.²³

The full spectrum XPS and associated elemental analysis (Figure S4) confirm the existence of C, K, O and F in Ti₃C₂ MNRs. It also evidenced the large enhancement of the O content which becomes over twice the initial value after the KOH treatment, indicating that the nanoribbon edges are rich in OH groups.

In the C 1s region (Figure 2b), the characteristic peaks of K2p3/2 at 292.4 eV and K2p1/2 at 295.2 eV are present only in Ti₃C₂ MNRs, but K presence was not detected in Ti₃C₂ MNSs neither in Ti₃AlC₂. This is consistent with XPS elemental analysis (Figure S4b). This accounts for the alkalization of MNRs, consistent with XRD measurement. However, the K atoms do not enter in the Ti₃C₂ MNRs structure to occupy the anion sites, as confirmed by analysis of the lattice spacing of (002) plane in XRD diffractograms.

After the treatment by KOH, the intensity of the XPS Ti-F peaks decreased markedly (Figure S4), while the contents of -OH on the surface increases significantly, indicating that a large amount of -F terminal groups were replaced by hydroxyl groups and consequently the formation of O-terminated Ti₃C₂ MNRs.³¹ EDX analysis of Ti₃C₂ MNSs and Ti₃C₂ MNR samples confirm this indication (Figure S5). The comparison of the elemental composition by XPS and EDX (SEM) (Figures S4 and S5, respectively) show that after the treatment by KOH, the Ti/C ratio increases owing to the carbon corrosion by KOH. Being XPS detecting the surface composition with a depth less than about 5 nm while the detection depth for SEM is up to about 1µm, the comparison of Ti/C ratios measured by XPS and EDX indicates a preferential surface carbon removal by the KOH treatment. The EDX of MAX phase (Ti₃AlC₂) and Ti₃C₂ MNSs (Table S1) indicates also that the oxygen content is similar in these two samples.

Figure 2c and 2d report the XPS Ti₂p and O₁s regions for the Ti₃C₂ MNRs (top) and MNSs (bottom) samples, respectively. Deconvolution of the spectra is also reported according to Lian et al.²³ and Halim et al.³² For Ti₂p region, spectra were deconvoluted for Ti-C, Ti²⁺, Ti³⁺ and TiO₂ components, while for O₁s region spectra were deconvoluted in Ti-O and -OH components. Figure 2c well indicates that the relative content of TiC decreased after KOH treatment with part of TiC transformed into Ti²⁺ and Ti³⁺. This result is well consistent with the increase of O content commented before. Ti-F component also disappears after the MNSs to MNRs conversion. Figure 2d evidences that the conversion leads to a significant increase in the Ti-O component (note that the spectra of Ti₃C₂ MNSs are multiplied by a factor three in intensity).

The electrocatalytic measurements (at room temperature and ambient pressure) were performed in the flow reactor described before operating without a liquid electrolyte in the hemi-cell where the NRR reaction occurs. The flow of highly pure N₂ (further purified by passing through filters to capture eventual presence of NOₓ, NH₃ and other possible contaminants) is passed through the electrocatalytic hemi-cell with the ammonia formed being then recovered from the gas outlet stream by absorption in a 0.001 M H₂SO₄ solution. The amount of ammonia formed was detected by a spectrophotometric method reported in detail in the Supplementary Info. This method is highly sensitive and we consider preferable and more reliable with respect to alternative methods such as NMR, ion-selective electrodes or mass

spectrometry. Supplementary Info also describes the tests made to exclude the formation of hydrazine (N₂H₄) under our experimental conditions. The protons/electrons for the NRR reactions derive from water electrolysis occurring in the other hemi-cell of the electrocatalytic reactor. A Nafion membrane separates the two hemi-cells (see Figure S1).

A series of control tests were made to verify that ammonia forms from the N₂ present in the flowing gas-phase and not from other N-contaminants (see Figure S3). These tests include monitoring the change in ammonia formation by switching from N₂ to Ar or using labelled nitrogen. By feeding N₂ + H₂ at open circuit conditions, it was also verified that the catalytic activity (i.e. not related to electrocatalysis) was negligible. Figure S2 in the Supplementary Info reports the experimental protocol for NRR tests used in these experiments, to demonstrate that the detected NH₃ derives from the electrocatalytic reduction of N₂.

Based on cyclic voltammetry (CV) tests (Figure S6), we selected three voltages (in the range from -0.2V to -0.8V vs RHE) to screen the behaviour of Ti₃C₂ MNRs. Results are reported in Figure S7 and S8. The highest NH₃ yield was obtained at -0.5 V vs RHE. Current density at this voltage is about -1.5 µA and remain stable for at least 3h of continuous tests. The current density remains stable also in longer term tests (up to about 10h), showing that the electrocatalyst is stable under these experimental conditions. This result was also in well agreement with CV tests (see Figure S6). At more negative voltage (-0.8 V), the current density instead decreases from the initial -3.5 µA value to about -4.5 µA (after 2h), indicating thus an in-situ transformation during the electrocatalytic tests. At a voltage of -0.2 V, the current density (about -0.5 µA) is instead low, indicating low catalytic activity. Further tests were thus made at -0.5 V. Data reported refer to the behaviour determined after 3h of continuous tests.

<figure><img src="image_4.png" /><figcaption>**Figure 3** Ammonia formation rate and Faradaic efficiency with different electrodes at -0.5 V vs. RHE after 3 h of electrocatalytic tests at room temperature and ambient pressure.</figcaption></figure>

Figure 3 reports the comparison of the rate of ammonia formation per mg of electrocatalysts for the pristine Ti₃AlC₂, Ti₃C₂ MNSs and MNRs samples. Pristine Ti₃AlC₂ and Ti₃C₂ MNSs have a quite comparable low activity in NRR, while Ti₃C₂ MNRs show a more than 5 times higher activity. Faradaic efficiency also increases to about 2% after transformation to nanoribbon. A stable current density was shown for all samples, indicating a stable behaviour at the applied voltage at least for 3h of continuous tests. No significant changes in the sample characteristics were also observed by electron microscopy, XPS and XRD characterization
of these materials after the electrocatalytic tests (see Figure S9 and S10). The constant CV data during extended cycles also confirm this stability. These results thus show that morphological, structural, surface and reactivity characteristics of Ti₃C₂ MNRs remain unchanged at least for 10h of continuous electrocatalytic tests at -0.5V vs. RHE.

A linear relationship could be observed between the rate of ammonia formation in the three samples reported in Figure 3 and the amount of oxygen on the surface (atomic %) as detected by XPS measurements (Figure 4), suggesting a relationship between these two aspects.

<figure><img src="image_5.png" /><figcaption>**Figure 4** Relationship between ammonia formation rate Fat -0.5 V vs. RHE and atomic % of oxygen in the surface as measured by XPS.</figcaption></figure>

The relationship presented in Figure 4 agrees (among others) with (i) Xia et al.<sup>11</sup> indications that exposed Ti sites (Ti₃C₂OH) are responsible for the improved electron transfer, adsorption and activation of dinitrogen, (ii) theoretical results of Tang et al.<sup>33</sup> that exposed Ti atom close to extra oxygen vacancy are responsible for activity in (defective) MXenes electrocatalysts, (iii) Jin et al.<sup>34</sup> indications that OH-rich MXenes (Ti₃C₂OH) show high NRR performances and (iv) Xia et al.<sup>35</sup> result that surface hydroxyl modification of MXene Ti₃C₂ facilitates the electron transfer and the adsorption and activation of dinitrogen. Therefore, this work shows that the transformation from a 2D-like morphology (nanosheets) to a 3D-like morphology (nanoribbons) leads to a large improvement in the NRR activity, due to an enhanced formation of active sites (likely Ti₃C₂OH) not blocked by F atoms.

To compare these data with literature, Table S2 reports a comparison of reaction conditions, ammonia formation rate and Faradaic selectivity of selected state-of-the-art literature results on NRR, organized in four classes of electrocatalytic materials: (a) MXenes, (b) modified and composite electrocatalysts based on MXenes, and electrocatalysts based on (c) noble metals or (d) transition metal oxides/sulphide. The comparison shows that particularly with respect to MXenes electrocatalysts, the electrocatalysts reported here well compares with other published, taking into account of the differences in the operative conditions, and the use here of an electrocatalytic reactor without liquid electrolyte differently from the other cases. Note, in addition, that the scope in this work is not to show record performances, but instead to analyse the role of the conversion from 2D (nanosheet) to 3D-like (nanoribbon) morphology in Ti₃C₂ MXenes.

For a further comparison, some selected results will be compared here. Luo et al.<sup>16</sup> reported for MXene (Ti₃C₂Tₓ)

nanosheets a maximum Faradic efficiency of 4.62% and a NH₃ yield rate of 2.7 µg·h⁻¹·mg<sub>CAT</sub>⁻¹ at a best potential of -0.1 vs. RHE. Xia et al.<sup>11</sup> indicated as best performances (Ti₃C₂ with an increased amount of surface hydroxyl moieties) a yield rate of NH₃ of 1.71 µg·h⁻¹·cm⁻² with a Faradaic efficiency of about 7%. These performances were in line with those indicated for analogous samples in the reviews by Sun et al.<sup>36</sup> and Li and Wu.<sup>37</sup> We may thus conclude that data reported in Figures 3 and 4 are in line with those earlier reported for Ti₃C₂ nanosheet-type materials, and thus the results reported here evidence a significant enhancement in NRR activity passing from nanosheet to nanoribbon-type morphology. This is related to the formation of OH-rich Ti₃C₂ MXene. This is in agreement with previous literature indications and theoretical studies, but here is for the first time demonstrated the presence of a linear relationship between ammonia formation rate and amount of oxygen on the surface of Ti₃C₂ MXene.

This result evidences that a 2D (nanosheet) morphology is not necessary in MXene materials to show NRR activity, and a different morphology (nanoribbon), not having the same basal planes and type of edges, show instead an about five-time higher NRR activity. Characterization data indicate that in nanoribbon morphology, there is a preferential formation of exposed Ti-O sites, which various studies have indicated as responsible for improved electron transfer, adsorption, and activation of dinitrogen.<sup>11,34,35</sup> Present data agree with this interpretation, and evidence for the first time the presence of a linear relationship between ammonia formation rate and amount of oxygen on the surface of Ti₃C₂ MXene.

## Acknowledgements

This work was made in the frame of the ERC Synergy SCOPE (project 810182), NSFC of China (21972140, 91645117 and 21872144), and PRIN 2017 MULTI-e project nr. 20179337R7, which are gratefully acknowledged. The work was also co-funded through a SINCHEM Grant. SINCHEM is a Joint Doctorate programme selected under the Erasmus Mundus Action 1 Programme (FPA 2013-0037). YL acknowledges the finical supports from LiaoNing Revitalization Talents Program (XLYC1907053) and CAS Youth Innovation Promotion Association (2018220).

**Keywords:** MXenes • N₂ fixation • Metal carbides • Nanosheets
• Nanoribbons

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