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Article

Construction of a Two-Dimensional GO/Ti3C2TX Composite Membrane and Investigation of Mg2+/Li+ Separation Performance

by
Zhenhua Feng
1,2,
Chengwen Liu
3,
Binbin Tang
1,2,
Xiaojun Yang
1,2,*,
Wenjie Jiang
1,2,
Peng Wang
4,
Xianjun Tang
4,
Hongshan Wang
3,
Xiangdong Zeng
3 and
Guangyong Zeng
3,*
1
Evaluation and Utilization of Strategic Rare Metals and Rare Earth Resource Key Laboratory of Sichuan Province, Chengdu Mineral Resources Supervision and Testing Center, Ministry of Land and Resources, Chengdu 610081, China
2
Chengdu Analytical & Testing Center for Mineral and Rocks, Sichuan Bureau of Geology and Mineral Resources, Chengdu 610081, China
3
College of Materials and Chemistry & Chemical Engineering, Chengdu University of Technology, Chengdu 610059, China
4
Sichuan Salt Geology Drilling Team (Sichuan Mineral Salt Mining Engineering Technology Research Center), Zigong 643000, China
*
Authors to whom correspondence should be addressed.
Nanomaterials 2023, 13(20), 2777; https://doi.org/10.3390/nano13202777
Submission received: 19 September 2023 / Revised: 9 October 2023 / Accepted: 14 October 2023 / Published: 17 October 2023
(This article belongs to the Special Issue Two-Dimensional Materials Membrane and Adsorbent for Wastewater Treatment)
Browse Figures
Review Reports Versions Notes

Abstract

:
Graphene oxide (GO) two-dimensional (2D) membranes with unique layer structures and tunable layer spacing have special advantages and great potential in the field of water treatment. However, GO membranes face the issues of weak anti-swelling ability as well as poor permeability. We prepared GO/Ti3C2TX 2D composite membranes with 2D/2D structures by intercalating Ti3C2TX nanosheets with slightly smaller sizes into GO membranes. Ti3C2TX intercalation can effectively expand the layer spacing of GO, thereby substantially enhancing the flux of the composite membrane (2.82 to 6.35 L·m−2·h−1). Moreover, the GO/Ti3C2TX composite membrane exhibited a good Mg2+/Li+ separation capability. For the simulated brine, the separation factor of M2 was 3.81, and the salt solution flux was as high as 5.26 L·m−2·h−1. Meanwhile, the incorporation of Ti3C2TX nanosheets significantly improved the stability of GO/Ti3C2TX membranes in different pH environments. This study provides a unique insight into the preparation of highly permeable and ion-selective GO membranes.

1. Introduction

With the vigorous growth of the new energy industry in recent years, lithium-ion batteries have become an industry hot spot [1,2,3]. This is leading to an increase in demand for lithium resources worldwide. However, the cost of extracting lithium from lithium ores using traditional methods is too high, and the environmental pollution is more serious. Therefore, the exploitation of lithium in liquid mines such as salt lakes has become one of the most effective ways to alleviate the current shortage of lithium resources [4,5]. Traditional lithium extraction techniques from salt lakes include precipitation, ion exchange, adsorption, and extraction. However, the above process has shortcomings such as high energy consumption, complex operation, and environmental problems [6,7]. Hence, the development of an efficient and green method for lithium extraction is of great significance.
Membrane technology is a separation and purification method with a simple process, low energy consumption, less use of chemical reagents, and a green environment [8,9]. There are more and more studies showing that membrane technology can be used for the extraction of lithium from lithium-containing solutions [10]. However, the membrane still faces problems such as low permeability, easy pollution of the membrane surface, and poor selectivity of lithium ions [3,11,12]. Common commercial membranes are dominated by inorganic material membranes and organic polymer membranes. The complexity of the preparation process of inorganic membranes leads to their high cost, while the poor mechanical strength of polymer membranes and the serious problem of membrane contamination lead to a short service life [13]. The trade-off effect of membranes restricts the improvement of their separation efficiency. In recent years, emerging 2D materials have provided new directions for the selection of high-performance membrane materials [14]. Two-dimensional materials represented by graphene oxide (GO), MoS2, and metal-organic frameworks can be stacked in a layer-by-layer fashion to form 2D layered membranes with nano/sub-nano channels [15]. GO is a typical two-dimensional layered nanosheet containing many epoxy, carboxyl, and hydroxyl groups on the surface and edge portions of GO nanosheets [16]. This enables GO to have excellent hydrophilicity and chemical modification properties. These functional groups can provide binding sites for the targets during the separation process, making GO membranes possess a good separation effect in the case of combined-size screening [17,18]. However, the functional groups of GO tend to generate hydrogen bonds between water molecules, thus increasing the osmotic resistance [19,20]. Moreover, the distance between layers of GO nanosheets is small (∼8 Å), so the permeability of membranes based only on GO is poor [21,22]. To solve this challenge, researchers have realized the enhancement of GO membrane permeation performance by dopamine-modified GO [23], MoS2 nanosheet doping [19], and chitosan coating [24]. In addition, GO nanosheets are prone to interact with water molecules in aqueous systems, leading to the swelling of GO membranes [25,26,27,28,29]. This is a difficult problem, limiting the application of GO membranes. Xi et al. [30] reduced GO to rGO, thus reducing the oxygen-containing functional groups of GO membranes. This resulted in a greatly enhanced stability of GO membranes doped with partially rGO nanosheets.
MXene is a general term for transition metal carbon/nitrides that exhibit a 2D nanosheet structure. It is characterized by large lateral size and ultra-thin thickness (the atomic level), a high specific surface area, and abundant hydrophilic groups (-F -O, -OH) [31,32]. Therefore, MXene has a wide range of applications in the fields of energy [33,34], catalysis, electrochemistry [35], environment [36,37], and biology [38]. The general formula of MXene can be expressed as Mn+1XnTx, which can be prepared by etching the precursor MAX phase (Mn+1AXn). M represents a transition metal element, A is aluminum or silicon, and X represents a carbon or nitrogen element. Tx is a surface functional group of MXene nanosheets (n = 1, 2, 3) [39,40]. The existing studies have shown that 2D membranes obtained by stacking MXene nanosheets have good permeability. MXene composite membranes have unique two-dimensional channels, excellent hydrophilicity, and chemical modifiability. They are widely used in oil-water separation [41], dye wastewater treatment [42], seawater desalination [43,44], and pharmaceutical wastewater treatment [45]. Ren et al. [46] constructed 2D MXene membranes on PVDF substrate membranes using vacuum filtration. The water flux was as high as 37.4 L·m−2·h−1·bar−1 and exhibited good selectivity for MB, Al3+, Mg2+, and Ca2+.
In this work, we obtained GO/Ti3C2TX membranes prepared by pressure-assisted filtration on the Polyethersulfone (PES) substrate. Owing to the small size of MXene nanosheets, which can be inserted into the interlayer of GO, Ti3C2TX nanosheets can be combined with GO through van der Waals force interaction. Moreover, Ti3C2TX can compensate for the non-selective defects caused by the stacking of GO layers, thus extending the path of ions in the interlayer nano-channels (improving the ion rejection of the composite membrane). The characterization of GO/Ti3C2TX composite membranes showed that Ti3C2TX was uniformly dispersed inside the composite membranes, and the GO/Ti3C2TX membranes still retained the lamellar structure. The layer spacing of GO/Ti3C2TX membranes was increased, which effectively increased the pure water flux of GO/Ti3C2TX membranes. In addition, GO/Ti3C2TX composite membranes presented high Mg2+ rejection and excellent Li+ permeability. The GO/Ti3C2TX membranes showed good Mg2+/Li+ selectivity for a mixed solution of MgCl2 and LiCl (Mg2+/Li+ mass ratio = 20). In addition, the introduction of Ti3C2TX nanosheets decreased the repulsion between the GO layers. Hence, the GO/Ti3C2TX membrane possesses better stability in water than the pure GO membrane.

2. Materials and Methods

2.1. Materials

Ti3AlC2 was purchased from Jilin 11 Technology Co. (Jilin, China). LiF, HCl, and NaNO3 were provided by Aladdin (Shanghai, China). KMnO4 and anhydrous MgCl2 were purchased from Chengdu Kelong (Chengdu, China). Anhydrous LiCl, H2SO4, and H2O2 were provided by Shanghai Adamas Reagent (Shanghai, China). PES microfiltration membranes (0.22 µm) were purchased from Tianjin Jinteng (Tianjin, China), and NaOH was purchased from Macklin Reagent (Shanghai, China).

2.2. Fabrication of GO

GO was prepared by the modified Hummers’ method [47]. Specifically, NaNO3 and H2SO4 were mixed in a beaker, and then a certain amount of natural graphite powder was added and stirred to obtain pre-oxidized graphite (2.5 h). Subsequently, KMnO4 was gradually incorporated into the above solution and magnetically stirred for 1 h. A H2O2 solution was added for further oxidation. The mixture was then centrifuged (3500 rpm) and washed with DI water until the solution had a pH = 7 to remove impurities and residual acid. Finally, GO nanosheets were obtained by ultrasonically peeling off multilayers of GO, and freeze-drying was used to obtain GO powder.

2.3. Preparation of Ti3C2TX Nanosheets

2D Ti3C2TX was fabricated by chemical etching the MAX phase using ultrasound-assisted stripping with a mixed solution of LiF + HCl [48,49]. First, 50 mL of HCl (9 M) was added to a polytetrafluoroethylene beaker, followed by the incorporation of 0.6 g of LiF into the HCl solution, stirring continuously until completely dissolved. Then, 0.5 g of Ti3AlC2 was added to the beaker and magnetically stirred at 30 °C for 28 h. The unstripped precipitate was separated from the supernatant by means of centrifugation (5000 rpm) and then washed several times repeatedly using deionized (DI) water until the supernatant pH > 6. The multilayered Ti3C2TX powder was obtained after drying at 50 °C. Subsequently, the multilayered Ti3C2TX nanosheets were added to DI water and ultrasonically stripped under a nitrogen atmosphere for 3 h to obtain monolayered Ti3C2TX nanosheets (25 °C). Finally, the multilayer Ti3C2TX was removed by centrifugation at 5000 rpm, and the supernatant was collected and freeze-dried for 30 h to obtain monolayer Ti3C2TX nanosheets.

2.4. Construction of GO/Ti3C2TX Composite Membranes

As shown in Figure 1, the GO nanosheets were first dispersed in 50 mL of DI water and ultrasonic for 20 min to obtain a homogeneous dispersion; in addition, the Ti3C2TX powder was added to another beaker containing 50 mL of DI water and ultrasonic for 15 min to make it well-dispersed. Then, the GO dispersion was mixed with the Ti3C2TX dispersion, and the GO/Ti3C2TX dispersion was obtained by sonication for another 15 min. The above dispersion was filtered onto a PES microfiltration membrane through a dead-end filtration device, and the GO/Ti3C2TX composite membrane was finally obtained. The ratio of GO to Ti3C2TX in the composite membrane is shown in Table 1.

2.5. Characterization of Membranes

The crystal structures of MAX, Ti3C2TX, and GO powders, as well as the interlayer spacing variation of GO/Ti3C2TX membranes, were characterized by X-ray diffraction (XRD). The elemental content of the composite membrane surface was tested by X-ray photoelectron spectroscopy (XPS). Scanning electron microscopy (SEM) was used to investigate the microscopic morphology of GO, MAX phase, and Ti3C2TX, as well as the GO/Ti3C2TX membranes. In addition, the hydrophilicity of the membrane surface was evaluated by means of a contact angle meter, and the contact angle was obtained by averaging three tests per membrane.

2.6. Membrane Performance Testing

The permeability and Mg2+/Li+ separation ability of the composite membranes were tested using a laboratory-constructed dead-end filtration unit (effective area of 12.56 cm−2). First, all membranes were pre-pressurized with DI water at 2.5 bar for 30 min. The flux (F: L·m−2·h−1) of the membrane was tested at 2 bar, and the volume of deionized water on the permeate side was collected and tested by Equation (1):
F = V A × t
where V (L) represents the permeate volume, A is the permeate area (m2), and t (h) represents the tested time for permeation.
Tested with 1 g/L LiCl and MgCl2 solutions to show the separation ability of membranes, respectively, and the rejection (R%) was tested by Equation (2):
R ( % ) = 1 − C p C f × 100 %
where Cf is the ion concentration on the feed side and Cp is the ion concentration in the permeate. A conductivity meter is used to test the conductivity of the solution before and after permeation to derive the salt concentration (DDS-307A).
The Mg2+/Li+ selectivity of the composite membrane was tested using a mixed solution of MgCl2 and LiCl (2 g/L), where the Mg2+/Li+ mass ratio was 20. The Mg2+/Li+ selectivity of the composite membrane was evaluated by the separation factor SLi,Mg, as in Equation (3):
S L i , M g = C L i , p / C M g , p C L i , f / C M g , f
where CLi,p is the concentration of Li+ in the permeate solution and CMg,p is Mg2+ on the permeate solution; CLi,f is the concentration of Li+ in the feed solution and CMg,f is Mg2+ on the feed side. Inductively coupled plasma optical emission spectroscopy (ICP-OES) was used to test the concentration of each ion in the salt solution before and after the permeate process.

3. Results and Discussion

3.1. Characterization of GO and Ti3C2TX Nanosheets

Figure 2a shows the XRD spectra of GO, Ti3AlC2, and Ti3C2Tx. A narrower peak (the characteristic peak of GO nanosheets) was presented at 2θ = 10.5° (001), which proved the successful synthesis of GO. The XRD results of Ti3C2Tx showed that the intensity of the 104 peak was much weakened compared to that of Ti3AlC2, which implied that the Al atomic layer of Ti3AlC2 was successfully etched. Moreover, the 002 peak of Ti3C2Tx shifted from 9.5° to 6.1° for Ti3AlC2, which indicated an increase in its interlayer spacing. All the above results demonstrated the successful synthesis of GO and Ti3C2TX nanosheets. Figure 2b reveals the morphology of tightly stacked GO nanosheets. The MAX phase (Figure 2c) is a larger-sized bulk structure with tighter layers. The Ti3C2TX nanosheets obtained by etching are sparser and show a clear layer structure (Figure 2d).
Figure 3a,b shows the surface of the original GO membrane (M0) at different multiplicities. M0 exhibited a large number of wrinkled structures, which are due to the flexible GO nanosheets with larger sizes when stacked [22]. And its surface is relatively smoother, without obvious defects. Observation of the cross-section of the M0 indicated that the GO nanosheets were arranged in a very regular manner. The M0 exhibited a typical 2D layered structure, with layers stacked densely. It is the nano-restricted domain channels created by the stacking of GO nanosheets on top of each other that allow GO membranes to trap targets larger than their layer spacing (Figure 3c,d). After intercalation into the GO membrane by Ti3C2TX nanosheets, the surface of the M2 was rougher, and the appearance of lamellar Ti3C2TX on its surface can be observed. However, the M2 still showed more folds, which indicated that its overall structure had not been changed (Figure 3e,f). The cross-sectional area of the M2 showed an increase in the thickness of their 2D-separated layers, and their lamellar structure was sparser than that of the M0. In addition, Ti3C2TX nanosheets with smaller sizes can be observed between the layers, which indicates the successful intercalation of Ti3C2TX (Figure 3g,h).
Figure 4 shows the EDS-mapping image of the M2, and it can be clearly observed that the Ti and F elements were more evenly distributed on the top of the membrane. This demonstrated that the Ti3C2TX nanosheets were uniformly dispersed in the GO membrane.
In the XPS spectra of M0, the fitted peaks of C 1s and O 1s appeared at 284.8 eV and 530 eV, which was consistent with the literature reports [50,51]. After the addition of Ti3C2TX, the fitted peaks at 682.4 eV and 457 eV corresponded to F 1s and Ti 2p, respectively (Figure 5a) [52]. The above results demonstrated the successful introduction of Ti3C2TX nanosheets into GO. The membrane surfaces of M0 and M2 were further analyzed using high-resolution C 1 spectroscopy. The 284.8 eV, 286.9 eV, and 288.5 eV in Figure 5b correspond to the C-C/C=C, C-O, and C=O/COOH present in GO nanosheets [53], respectively (Figure 5b). The C 1s spectrum of the M2 (Figure 5c) showed an additional fitted peak at 282.3 eV, which corresponds to the C-Ti in the Ti3C2TX nanosheets [29]. The convolution peaks appearing at 455.8, 458.7, 460.2, 461.6, and 464.4 eV correspond to C-Ti-(O, OH), Tix-Oy, TiO2, Ti-Cx, and C-Ti-F (Figure 5d) [54]. The surface element contents of M0 and M2 are shown in Table 2. The addition of F and Ti elements in M2 proved that Ti3C2TX was successfully doped in the GO layer.
Figure 6 shows the XRD patterns of M0 and M2. For the M0, the characteristic peak of GO nanosheets was located at 2θ = 11.1°. The layer spacing d = 7.94 Å of the M0 at this time was calculated by Bragg’s equation. After the intercalation by Ti3C2TX, the characteristic peak of M2 was slightly shifted to the left at 2θ = 10.4°, and the layer spacing d = 8.5 Å of the M2. The above results proved that the 2D Ti3C2TX nanosheets could enter the interlayer of GO, which led to the widening of layer spacing in the GO 2D membranes. This will reduce the permeation resistance of water molecules and effectively enhance the water flux [55].

3.2. The Performance of GO/Ti3C2TX Composite Membrane

Figure 7a shows the water contact angle (WCA) of different membrane surfaces. According to reports [56], the lower the water contact angle on the membrane surface, the better hydrophilicity the membrane possesses. The CA of the original M0 was 39°, indicating that the GO membrane was more hydrophilic. Since GO nanosheets contain a large number of hydrophilic groups such as hydroxyl, carboxyl, and epoxy groups, these groups can have hydrogen bonding interactions with water molecules, thus allowing the membrane surface to absorb more water molecules and accelerating the formation of the hydration layer. After adding Ti3C2TX to the GO membrane, the CA of all GO/Ti3C2TX membranes was higher than M0. Since the surface hydrophilic functional groups of Ti3C2TX nanosheets were less than those of GO, the hydrophilicity of GO/Ti3C2TX membranes was weaker compared with M0.
Figure 7b shows the water flux of the original GO membranes loaded with different contents. The pure water flux of the GO membrane gradually decreased with the increase in GO content. The GO membrane loaded with 2 mg showed the lowest water flux (2.27 L·m−2·h−1), and due to the small layer spacing of the 2D GO membrane, its permeability is usually poor compared to other 2D membranes (such as 2D Ti3C2TX membranes and MoS2 membranes). In addition, the increase in GO loading significantly increased the thickness of the separation layer, leading to enhanced permeation resistance. Hence, the permeability of the membrane gradually decreased. In addition, the separation ability of GO membranes with different contents was tested using 1 g/L MgCl2. From Figure 7c, it can be observed that the flux of the MgCl2 salt solution showed a decreasing trend as the GO loading increased, which was similar to its pure water flux changes (11 to 1.93 L·m−2·h−1). The retention of MgCl2 by the GO membrane was enhanced with increasing GO content (42.1% to 63.3%). Since the hydration diameter of Mg2+ is 8.56 Å, it is slightly larger than the layer spacing of the GO membrane (7.94 Å). Under the action of size screening [57], the larger-sized Mg2+ is intercepted by the GO membrane, which achieves better Mg2+ retention. However, the results showed that the permeability of GO membranes was bound to be poor if they were to realize a good ion retention effect. This indicated that the separation effect of the GO membrane was always constrained by the trade-off effect.
After mixing Ti3C2TX nanosheets in 2D GO-based membranes, the flux of different ratios of GO/Ti3C2TX membranes was enhanced (Figure 7a). It increased from 2.8 L·m−2·h−1 in M0 to the highest 13.2 L·m−2·h−1 in M4. This was attributed to the fact that the intercalation of Ti3C2TX nanosheets effectively enhanced the layer spacing of the GO membrane. The transport resistance of water molecules was reduced, resulting in a substantial increase in the permeability of the GO/Ti3C2TX membrane. To evaluate the separation effect of GO/Ti3C2TX membranes, a 1 g/L MgCl2 solution was used for testing. As shown in Figure 7d, the Mg2+ rejection of M1 was similar to that of M0. Since the layer spacing of the GO/Ti3C2TX membrane has not changed significantly currently, the rejection of Mg2+ by M2 was increased to 65.2%, and the flux was twice that of M0. The enhancement of Mg2+ rejection was mainly due to the addition of Ti3C2TX to increase the thickness of the membrane, while the separation capacity of M2 was enhanced by the synergistic effect of size-sieving action and adsorption [58]. With the excessive addition of Ti3C2TX, the MgCl2 flux of M3 and M4 increased greatly, but the rejection of Mg2+ also showed a significant decline. This was because too many Ti3C2TX nanosheets may cause the layer spacing of the GO/Ti3C2TX membrane to be larger than the hydration diameter of Mg2+. In addition, all GO/Ti3C2TX membranes showed low rejection of LiCl (Figure 7e). This was attributed to Li+ having a smaller hydration diameter (7.64 Å) [59]. The permeability of the different membranes was combined, as was the difference in rejection for Mg2+ and Li+. M2 was selected as the best membrane to investigate its Mg2+/Li+ separation ability.
A mixed solution of MgCl2 and LiCl (Mg2+/Li+ mass ratio of 20, 2 g/L) was used as a simulated brine. As shown in Figure 7f, the flux of the salt solution of M0 was 2.5 L·m−2·h−1, and the SLi,Mg was 3.35. The permeability of GO/Ti3C2TX membranes with different ratios was enhanced by Ti3C2TX intercalation modification. M2 had the highest separation ability (SLi,Mg = 3.81), while the permeability (5.26 L·m−2·h−1) was enhanced by ~100% compared to M0. With the further addition of Ti3C2TX, the SLi,Mg of both M3 and M4 were significantly lower, despite the substantial increase in permeability. The M2 had a suitable layer spacing (8.5 Å) after being modified with Ti3C2TX. Compared to the original M0, the increased layer spacing of M2 can significantly reduce the permeation resistance of water molecules and increase the flux of the membrane. In addition, the layer spacing of M2 was slightly smaller than the hydration diameter of Mg2+. This made M2 possess better Mg2+ rejection. On the other hand, the layer spacing of M2 is larger than the hydration diameter of Li+, so M2 has excellent permeability to Li+. In summary, M2 possessed good permeability and Mg2+/Li+ separation ability.
Since 2D GO membranes are highly susceptible to swelling in water, this can significantly reduce the service life of the membranes [60]. It was tested for the stability of M0 and M2 to evaluate their anti-swelling ability under different conditions of use (Figure 8). M0 and M2 were immersed in the corresponding acidic, neutral, and alkaline solutions at pH = 3, 7, and 11. It was clearly found that the surface of the M0 gradually changed from yellow to brown with the increase in immersion time. The separation layer under the three different pHs occurred with different degrees of detachment and disintegration. For M2, the membrane surface color did not change after 14 days of immersion in different acidic and alkaline conditions. The surface separation layer was structurally complete and did not produce peeling or cracking. The above experimental results indicated that the doping of Ti3C2TX nanosheets will effectively improve the anti-swelling ability of the GO/Ti3C2TX membrane, thus enhancing its stability in water. Since Ti3C2TX nanosheets weaken the mutual repulsion between the GO layers, the separate layer is more stable [51,61].

4. Conclusions

In this work, a novel two-dimensional GO/Ti3C2TX composite membrane was prepared by pressure-assisted filtration and investigated for its Mg2+/Li+ separation performance. SEM, XRD, and XPS were used to characterize the microscopic morphology and physicochemical properties of the GO/Ti3C2TX membrane and to demonstrate the successful intercalation of Ti3C2TX nanosheets into the GO membrane. The permeation performance of the optimal GO/Ti3C2TX membrane (M2) was significantly improved (from 2.82 to 6.35 L·m−2·h−1) compared to the original GO membrane, which is almost three times better. Ti3C2TX nanosheets functioned as an intercalation to expand the layer spacing in GO membranes, which made the two-dimensional layered structure of the composite membranes sparser. Thus, the water permeability of the GO/Ti3C2TX membrane was increased. In addition, the enhanced layer spacing (8.5 Å) of GO/Ti3C2TX membranes was still smaller than the hydration diameter of Mg2+. The size-sieving effect made the composite membrane possess a good Mg2+ rejection and a very low Li+ rejection. This resulted in a good Mg2+/Li+ selective separation (SLi,Mg = 3.8). The GO/Ti3C2TX membrane also exhibited excellent anti-swelling ability and was more stable than the GO membrane under different acid-base conditions. This 2D/2D combination provides a new idea for the further development of 2D GO membranes in the field of Mg2+/Li+ separation.

Author Contributions

Writing—original draft, data curation, Z.F.; investigation, formal analysis, C.L.; methodology, B.T.; supervision, funding acquisition, X.Y.; software, W.J.; resources, P.W.; validation, X.T.; visualization, H.W.; writing—review and editing, X.Z.; supervision, project administration, G.Z. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Sichuan Institute of Geological Survey (SDDY-Z2022013, SCIGS-CZDZX-2023001); Open fund of Evaluation and Utilization of Strategic Rare Metals and Rare Earth Resource Key Laboratory of Sichuan Province (DYY-ZDSYS-202202).

Data Availability Statement

The data that supports the findings of this study is available.

Conflicts of Interest

The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

References

  1. Zhou, Z.; Huang, J.; Li, M.; Lu, Y. The Dynamic Evolution of the Material Flow of Lithium Resources in China. Sustainability 2022, 14, 16928. [Google Scholar] [CrossRef]
  2. Murodjon, S.; Tianlong Deng, M.S.; Tianlong, D. Lithium Recovery from Water Resources by Ion Exchange and Sorption Method. J. Chem. Soc. Pak. 2021, 43, 406. [Google Scholar] [CrossRef]
  3. Liu, Y.; Ma, B.; Lu, Y.; Wang, C.; Chen, Y. A review of lithium extraction from natural resources. Int. J. Miner. Metall. Mater. 2023, 30, 209–224. [Google Scholar] [CrossRef]
  4. Li, J.; Zou, T.; Liu, X.; Wang, D.; Ding, X. The Metallogenetic Regularities of Lithium Deposits in China. Acta Geol. Sin.-Engl. Ed. 2015, 89, 652–670. [Google Scholar] [CrossRef]
  5. Gruber, P.W.; Medina, P.A.; Keoleian, G.A.; Kesler, S.E.; Everson, M.P.; Wallington, T.J. Global Lithium Availability A Constraint for Electric Vehicles? J. Ind. Ecol. 2011, 15, 760–775. [Google Scholar] [CrossRef]
  6. Dessemond, C.; Lajoie-Leroux, F.; Soucy, G.; Laroche, N.; Magnan, J.-F. Spodumene: The Lithium Market, Resources and Processes. Minerals 2019, 9, 334. [Google Scholar] [CrossRef]
  7. Ambrose, H.; Kendall, A. Understanding the future of lithium: Part 1, resource model. J. Ind. Ecol. 2020, 24, 80–89. [Google Scholar] [CrossRef]
  8. Liu, G.; Jin, W. Pervaporation membrane materials: Recent trends and perspectives. J. Membr. Sci. 2021, 636, 119557. [Google Scholar] [CrossRef]
  9. Bodzek, M.; Konieczny, K.; Kwiecinska-Mydlak, A. Application of nanotechnology and nanomaterials in water and wastewater treatment: Membranes, photocatalysis and disinfection. Desalination Water Treat. 2020, 186, 88–106. [Google Scholar] [CrossRef]
  10. Peng, H.; Zhao, Q. A Nano-Heterogeneous Membrane for Efficient Separation of Lithium from High Magnesium/Lithium Ratio Brine. Adv. Funct. Mater. 2021, 31, 2009430. [Google Scholar] [CrossRef]
  11. Yuan, H.; Liu, J.; Zhang, X.; Chen, L.; Zhang, Q.; Ma, L. Recent advances in membrane-based materials for desalination and gas separation. J. Clean. Prod. 2023, 387, 135845. [Google Scholar] [CrossRef]
  12. Wang, S.; Li, X.; Wu, H.; Tian, Z.; Xin, Q.; He, G.; Peng, D.; Chen, S.; Yin, Y.; Jiang, Z.; et al. Advances in high permeability polymer-based membrane materials for CO2 separations. Energy Environ. Sci. 2016, 9, 1863–1890. [Google Scholar] [CrossRef]
  13. Prasetya, N.; Himma, N.F.; Sutrisna, P.D.; Wenten, I.G.; Ladewig, B.P. A review on emerging organic-containing microporous material membranes for carbon capture and separation. Chem. Eng. J. 2020, 391, 123575. [Google Scholar] [CrossRef]
  14. Lin, Q.; Liu, Y.; Yang, Z.; He, Z.; Wang, H.; Zhang, L.; Belle Marie Yap Ang, M.; Zeng, G. Construction and application of two-dimensional MXene-based membranes for water treatment: A mini-review. Results Eng. 2022, 15, 100494. [Google Scholar] [CrossRef]
  15. Liu, G.; Jin, W.; Xu, N. Two-Dimensional-Material Membranes: A New Family of High-Performance Separation Membranes. Angew. Chem.-Int. Ed. 2016, 55, 13384–13397. [Google Scholar] [CrossRef] [PubMed]
  16. Zhang, M.; Guan, K.; Ji, Y.; Liu, G.; Jin, W.; Xu, N. Controllable ion transport by surface-charged graphene oxide membrane. Nat. Commun. 2019, 10, 1253. [Google Scholar] [CrossRef]
  17. Chong, J.Y.; Wang, B.; Mattevi, C.; Li, K. Dynamic microstructure of graphene oxide membranes and the permeation flux. J. Membr. Sci. 2018, 549, 385–392. [Google Scholar] [CrossRef]
  18. Zhang, M.; Sun, J.; Mao, Y.; Liu, G.; Jin, W. Effect of substrate on formation and nanofiltration performance of graphene oxide membranes. J. Membr. Sci. 2019, 574, 196–204. [Google Scholar] [CrossRef]
  19. Yadav, S.; Ibrar, I.; Altaee, A.; Samal, A.K.; Ghobadi, R.; Zhou, J. Feasibility of brackish water and landfill leachate treatment by GO/MoS2-PVA composite membranes. Sci. Total Environ. 2020, 745, 141088. [Google Scholar] [CrossRef]
  20. Liu, G.; Jin, W.; Xu, N. Graphene-based membranes. Chem. Soc. Rev. 2015, 44, 5016–5030. [Google Scholar] [CrossRef]
  21. Yu, L.; Zhang, Y.; Zhang, B.; Liu, J.; Zhang, H.; Song, C. Preparation and characterization of HPEI-GO/PES ultrafiltration membrane with antifouling and antibacterial properties. J. Membr. Sci. 2013, 447, 452–462. [Google Scholar] [CrossRef]
  22. Xu, Y.; Wu, M.; Yu, S.; Zhao, Y.; Gao, C.; Shen, J. Ultrathin and stable graphene oxide film via intercalation polymerization of polydopamine for preparation of digital inkjet printing dye. J. Membr. Sci. 2019, 586, 15–22. [Google Scholar] [CrossRef]
  23. Zhang, M.; Mao, Y.; Liu, G.; Liu, G.; Fan, Y.; Jin, W. Molecular Bridges Stabilize Graphene Oxide Membranes in Water. Angew. Chem.-Int. Ed. 2020, 59, 1689–1695. [Google Scholar] [CrossRef] [PubMed]
  24. Huang, K.; Liu, G.; Shen, J.; Chu, Z.; Zhou, H.; Gu, X.; Jin, W.; Xu, N. High-Efficiency Water-Transport Channels using the Synergistic Effect of a Hydrophilic Polymer and Graphene Oxide Laminates. Adv. Funct. Mater. 2015, 25, 5809–5815. [Google Scholar] [CrossRef]
  25. Ahmadi, H.; Zakertabrizi, M.; Hosseini, E.; Cha-Umpong, W.; Abdollahzadeh, M.; Korayem, A.H.; Chen, V.; Shon, H.K.; Asadnia, M.; Razmjou, A. Heterogeneous asymmetric passable cavities within graphene oxide nanochannels for highly efficient lithium sieving. Desalination 2022, 538, 115888. [Google Scholar] [CrossRef]
  26. Zeng, G.; Lin, Q.; Wei, K.; Liu, Y.; Zheng, S.; Zhan, Y.; He, S.; Patra, T.; Chiao, Y.-H. High-performing composite membrane based on dopamine-functionalized graphene oxide incorporated two-dimensional MXene nanosheets for water purification. J. Mater. Sci. 2021, 56, 6814–6829. [Google Scholar] [CrossRef]
  27. Ran, J.; Chu, C.; Pan, T.; Ding, L.; Cui, P.; Fu, C.-F.; Zhang, C.-L.; Xu, T. Non-covalent cross-linking to boost the stability and permeability of graphene-oxide-based membranes. J. Mater. Chem. A 2019, 7, 8085–8091. [Google Scholar] [CrossRef]
  28. Song, N.; Gao, X.; Ma, Z.; Wang, X.; Wei, Y.; Gao, C. A review of graphene-based separation membrane: Materials, characteristics, preparation and applications. Desalination 2018, 437, 59–72. [Google Scholar] [CrossRef]
  29. Wei, S.; Xie, Y.; Xing, Y.; Wang, L.; Ye, H.; Xiong, X.; Wang, S.; Han, K. Two-dimensional graphene Oxide/MXene composite lamellar membranes for efficient solvent permeation and molecular separation. J. Membr. Sci. 2019, 582, 414–422. [Google Scholar] [CrossRef]
  30. Xi, Y.-H.; Liu, Z.; Ji, J.; Wang, Y.; Faraj, Y.; Zhu, Y.; Xie, R.; Ju, X.-J.; Wang, W.; Lu, X.; et al. Graphene-based membranes with uniform 2D nanochannels for precise sieving of mono-/multi-valent metal ions. J. Membr. Sci. 2018, 550, 208–218. [Google Scholar] [CrossRef]
  31. Yang, Z.; Lin, Q.; Zeng, G.; Zhao, S.; Yan, G.; Ang, M.B.M.Y.; Chiao, Y.-H.; Pu, S. Ternary hetero-structured BiOBr/Bi2MoO6@MXene composite membrane: Construction and enhanced removal of antibiotics and dyes from water. J. Membr. Sci. 2022, 669, 121329. [Google Scholar] [CrossRef]
  32. Cheng, X.; Liao, J.; Xue, Y.; Lin, Q.; Yang, Z.; Yan, G.; Zeng, G.; Sengupta, A. Ultrahigh-flux and self-cleaning composite membrane based on BiOCl-PPy modified MXene nanosheets for contaminants removal from wastewater. J. Membr. Sci. 2022, 644, 120188. [Google Scholar] [CrossRef]
  33. Zhao, Q.-N.; Zhang, Y.-J.; Duan, Z.-H.; Wang, S.; Liu, C.; Jiang, Y.-D.; Tai, H.-L. A review on Ti3C2Tx-based nanomaterials: Synthesis and applications in gas and humidity sensors. Rare Met. 2020, 40, 1459–1476. [Google Scholar] [CrossRef]
  34. Chen, X.; Kong, Z.; Li, N.; Zhao, X.; Sun, C. Proposing the prospects of Ti3CN transition metal carbides (MXenes) as anodes of Li-ion batteries: A DFT study. Phys. Chem. Chem. Phys. 2016, 18, 32937–32943. [Google Scholar] [CrossRef]
  35. Yan, J.; Ren, C.E.; Maleski, K.; Hatter, C.B.; Anasori, B.; Urbankowski, P.; Sarycheva, A.; Gogotsi, Y. Flexible MXene/Graphene Films for Ultrafast Supercapacitors with Outstanding Volumetric Capacitance. Adv. Funct. Mater. 2017, 27, 1701264. [Google Scholar] [CrossRef]
  36. Mashtalir, O.; Cook, K.M.; Mochalin, V.N.; Crowe, M.; Barsoum, M.W.; Gogotsi, Y. Dye adsorption and decomposition on two-dimensional titanium carbide in aqueous media. J. Mater. Chem. A 2014, 2, 14334–14338. [Google Scholar] [CrossRef]
  37. Pasupuleti, K.S.; Thomas, A.M.; Vidyasagar, D.; Rao, V.N.; Yoon, S.-G.; Kim, Y.-H.; Kim, S.-G.; Kim, M.-D. ZnO@Ti3C2Tx MXene Hybrid Composite-Based Schottky-Barrier-Coated SAW Sensor for Effective Detection of Sub-ppb-Level NH3 at Room Temperature under UV Illumination. ACS Mater. Lett. 2023, 5, 2739–2746. [Google Scholar] [CrossRef]
  38. Qin, M.; Merzougui, C.; Su, Y.-m.; Li, Y.-f.; Chen, W.-y.; Huang, D. Recent developments in MXene and MXene/carbon composites for use in biomedical applications. New Carbon Mater. 2023, 38, 496–506. [Google Scholar] [CrossRef]
  39. Karahan, H.E.; Goh, K.; Zhang, C.; Yang, E.; Yıldırım, C.; Chuah, C.Y.; Ahunbay, M.G.; Lee, J.; Tantekin-Ersolmaz, Ş.B.; Chen, Y.; et al. MXene Materials for Designing Advanced Separation Membranes. Adv. Mater. 2020, 32, 1906697. [Google Scholar] [CrossRef]
  40. Ihsanullah, I. Potential of MXenes in Water Desalination: Current Status and Perspectives. Nano-Micro Lett. 2020, 12, 72. [Google Scholar] [CrossRef]
  41. Li, Z.-K.; Liu, Y.; Li, L.; Wei, Y.; Caro, J.; Wang, H. Ultra-thin titanium carbide (MXene) sheet membranes for high-efficient oil/water emulsions separation. J. Membr. Sci. 2019, 592, 117361. [Google Scholar] [CrossRef]
  42. Sagita, F.; Radiman, C.L.; Ledyastuti, M.; Khalil, M.; Kadja, G.T.M. Salt-modified MXene membrane for ultrafast and efficient cationic and anionic dyes removal. J. Water Process Eng. 2022, 49, 103133. [Google Scholar] [CrossRef]
  43. Ding, M.; Xu, H.; Chen, W.; Yang, G.; Kong, Q.; Ng, D.; Lin, T.; Xie, Z. 2D laminar maleic acid-crosslinked MXene membrane with tunable nanochannels for efficient and stable pervaporation desalination. J. Membr. Sci. 2020, 600, 117871. [Google Scholar] [CrossRef]
  44. Li, X.; Chen, L.; Chao, Y.; Zhu, L.; Luo, G.; Sun, J.; Jiang, L.; Zhu, W.; Liu, Z.; Xu, C. Highly selective separation of lithium with hierarchical porous lithium-ion sieve microsphere derived from MXene. Desalination 2022, 537, 115847. [Google Scholar] [CrossRef]
  45. Li, Z.K.; Wei, Y.; Gao, X.; Ding, L.; Lu, Z.; Deng, J.; Yang, X.; Caro, J.; Wang, H. Antibiotics Separation with MXene Membranes Based on Regularly Stacked High-Aspect-Ratio Nanosheets. Angew. Chem. Int. Ed. 2020, 59, 9751–9756. [Google Scholar] [CrossRef] [PubMed]
  46. Ren, C.E.; Hatzell, K.B.; Alhabeb, M.; Ling, Z.; Mahmoud, K.A.; Gogotsi, Y. Charge- and Size-Selective Ion Sieving through Ti3C2Tx MXene Membranes. J. Phys. Chem. Lett. 2015, 6, 4026–4031. [Google Scholar] [CrossRef]
  47. Zhu, Z.; Wang, L.; Xu, Y.; Li, Q.; Jiang, J.; Wang, X. Preparation and characteristics of graphene oxide-blending PVDF nanohybrid membranes and their applications for hazardous dye adsorption and rejection. J. Colloid Interface Sci. 2017, 504, 429–439. [Google Scholar] [CrossRef]
  48. Zeng, G.; He, Z.; Wan, T.; Wang, T.; Yang, Z.; Liu, Y.; Lin, Q.; Wang, Y.; Sengupta, A.; Pu, S. A self-cleaning photocatalytic composite membrane based on g-C3N4@MXene nanosheets for the removal of dyes and antibiotics from wastewater. Sep. Purif. Technol. 2022, 292, 121037. [Google Scholar] [CrossRef]
  49. Lin, Q.; Zeng, G.; Yan, G.; Luo, J.; Cheng, X.; Zhao, Z.; Li, H. Self-cleaning photocatalytic MXene composite membrane for synergistically enhanced water treatment: Oil/water separation and dyes removal. Chem. Eng. J. 2022, 427, 119058. [Google Scholar] [CrossRef]
  50. Liao, F.; Xu, Z.; Fan, Z.; Meng, Q.; Lv, B.; Ye, X.; Shen, C.; Zhang, G. Confined assembly of ultrathin dual-functionalized Z-MXene nanosheet intercalated GO nanofilms with controlled structure for size-selective permeation. J. Mater. Chem. A 2021, 9, 12236–12243. [Google Scholar] [CrossRef]
  51. Yin, Z.; Lu, Z.; Xu, Y.; Zhang, Y.; He, L.; Li, P.; Xiong, L.; Ding, L.; Wei, Y.; Wang, H. Supported MXene/GO Composite Membranes with Suppressed Swelling for Metal Ion Sieving. Membranes 2021, 11, 621. [Google Scholar] [CrossRef] [PubMed]
  52. Lin, Q.; Zeng, G.; Pu, S.; Yan, G.; Luo, J.; Wan, Y.; Zhao, Z. A dual regulation strategy for MXene-based composite membrane to achieve photocatalytic self-cleaning properties and multi-functional applications. Chem. Eng. J. 2022, 443, 136335. [Google Scholar] [CrossRef]
  53. Liu, T.; Liu, X.; Graham, N.; Yu, W.; Sun, K. Two-dimensional MXene incorporated graphene oxide composite membrane with enhanced water purification performance. J. Membr. Sci. 2020, 593, 117431. [Google Scholar] [CrossRef]
  54. Kang, K.M.; Kim, D.W.; Ren, C.E.; Cho, K.M.; Kim, S.J.; Choi, J.H.; Nam, Y.T.; Gogotsi, Y.; Jung, H.T. Selective Molecular Separation on Ti3C2Tx-Graphene Oxide Membranes during Pressure-Driven Filtration: Comparison with Graphene Oxide and MXenes. ACS Appl. Mater. Interfaces 2017, 9, 44687–44694. [Google Scholar] [CrossRef] [PubMed]
  55. Zeng, G.; Liu, Y.; Lin, Q.; Pu, S.; Zheng, S.; Ang, M.B.M.Y.; Chiao, Y.-H. Constructing composite membranes from functionalized metal organic frameworks integrated MXene intended for ultrafast oil/water emulsion separation. Sep. Purif. Technol. 2022, 293, 121052. [Google Scholar] [CrossRef]
  56. Liu, Y.; Lin, Q.; Zeng, G.; Zhang, L.; Zhou, Y.; Sengupta, A. Nature-inspired green method decorated MXene-based composite membrane for high-efficiency oil/water separation. Sep. Purif. Technol. 2022, 283, 120218. [Google Scholar] [CrossRef]
  57. Zhao, X.; Che, Y.; Mo, Y.; Huang, W.; Wang, C. Fabrication of PEI modified GO/MXene composite membrane and its application in removing metal cations from water. J. Membr. Sci. 2021, 640, 119847. [Google Scholar] [CrossRef]
  58. Ma, J.; Tang, X.; He, Y.; Fan, Y.; Chen, J.; Yu, H. Robust stable MoS2/GO filtration membrane for effective removal of dyes and salts from water with enhanced permeability. Desalination 2020, 480, 114328. [Google Scholar] [CrossRef]
  59. Xu, P.; Wang, W.; Qian, X.; Wang, H.; Guo, C.; Li, N.; Xu, Z.; Teng, K.; Wang, Z. Positive charged PEI-TMC composite nanofiltration membrane for separation of Li+ and Mg2+ from brine with high Mg2+/Li+ ratio. Desalination 2019, 449, 57–68. [Google Scholar] [CrossRef]
  60. Cheng, P.; Chen, Y.; Gu, Y.-H.; Yan, X.; Lang, W.-Z. Hybrid 2D WS2/GO nanofiltration membranes for finely molecular sieving. J. Membr. Sci. 2019, 591, 117308. [Google Scholar] [CrossRef]
  61. Zhang, P.; Gong, J.-L.; Zeng, G.-M.; Song, B.; Cao, W.; Liu, H.-Y.; Huan, S.-Y.; Peng, P. Novel “loose” GO/MoS2 composites membranes with enhanced permeability for effective salts and dyes rejection at low pressure. J. Membr. Sci. 2019, 574, 112–123. [Google Scholar] [CrossRef]
Nanomaterials 13 02777 g001
Figure 1. Schematic diagram of GO/Ti3C2TX composite membrane preparation.
Figure 1. Schematic diagram of GO/Ti3C2TX composite membrane preparation.
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Figure 2. (a) XRD pattern of MAX and Ti3C2TX; SEM images of (b) GO, (c) MAX, and (d) Ti3C2TX.
Figure 2. (a) XRD pattern of MAX and Ti3C2TX; SEM images of (b) GO, (c) MAX, and (d) Ti3C2TX.
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Figure 3. (a,b,e,f) surface and (c,d,g,h) cross-section of SEM images for M0 and M2.
Figure 3. (a,b,e,f) surface and (c,d,g,h) cross-section of SEM images for M0 and M2.
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Figure 4. EDS mapping of M2.
Figure 4. EDS mapping of M2.
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Figure 5. (a) XPS full spectra of M0 and M2; (b,c) High-resolution C 1s spectra of M0 and M2; (d) Ti 2p spectra of M2.
Figure 5. (a) XPS full spectra of M0 and M2; (b,c) High-resolution C 1s spectra of M0 and M2; (d) Ti 2p spectra of M2.
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Figure 6. XRD spectra of M0 and M2.
Figure 6. XRD spectra of M0 and M2.
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Figure 7. (a) CA and water flux of GO/Ti3C2TX membranes; (b,c) Water flux and MgCl2 separation ability with different content of GO membranes; (d,e) Separation performance of GO/Ti3C2TX membranes for MgCl2 and LiCl solutions; (f) Mg2+/Li+ separation ability of GO/Ti3C2TX membranes.
Figure 7. (a) CA and water flux of GO/Ti3C2TX membranes; (b,c) Water flux and MgCl2 separation ability with different content of GO membranes; (d,e) Separation performance of GO/Ti3C2TX membranes for MgCl2 and LiCl solutions; (f) Mg2+/Li+ separation ability of GO/Ti3C2TX membranes.
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Figure 8. Stability test of M0 and M2 under different conditions.
Figure 8. Stability test of M0 and M2 under different conditions.
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Table 1. Composition of different GO/Ti3C2TX composite membranes.
Table 1. Composition of different GO/Ti3C2TX composite membranes.
MembraneGO
(mg)		Ti3C2TX
(mg)
M01.50
M11.50.5
M21.51
M31.51.5
M41.52
Table 2. XPS analysis results shows elemental content on the M0 and M2 surfaces.
Table 2. XPS analysis results shows elemental content on the M0 and M2 surfaces.
MembraneC (%)O (%)Ti (%)F (%)
M072.127.900
M269.7428.240.971.05
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Feng, Z.; Liu, C.; Tang, B.; Yang, X.; Jiang, W.; Wang, P.; Tang, X.; Wang, H.; Zeng, X.; Zeng, G. Construction of a Two-Dimensional GO/Ti3C2TX Composite Membrane and Investigation of Mg2+/Li+ Separation Performance. Nanomaterials 2023, 13, 2777. https://doi.org/10.3390/nano13202777

AMA Style

Feng Z, Liu C, Tang B, Yang X, Jiang W, Wang P, Tang X, Wang H, Zeng X, Zeng G. Construction of a Two-Dimensional GO/Ti3C2TX Composite Membrane and Investigation of Mg2+/Li+ Separation Performance. Nanomaterials. 2023; 13(20):2777. https://doi.org/10.3390/nano13202777

Chicago/Turabian Style

Feng, Zhenhua, Chengwen Liu, Binbin Tang, Xiaojun Yang, Wenjie Jiang, Peng Wang, Xianjun Tang, Hongshan Wang, Xiangdong Zeng, and Guangyong Zeng. 2023. "Construction of a Two-Dimensional GO/Ti3C2TX Composite Membrane and Investigation of Mg2+/Li+ Separation Performance" Nanomaterials 13, no. 20: 2777. https://doi.org/10.3390/nano13202777

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