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Microsoft Word - AMO_TSTA_A_2597556.docxScience and Technology of Advanced MaterialsISSN: 1468-6996 (Print) 1878-5514 (Online) Journal homepage: www.tandfonline.com/journals/tsta20Are MXenes viable as conductive, transparentfilms for industrial applications?Tiezhu Guo, Shungui Deng, Rene Schneider, Chuanfang Zhang & Jakob HeierTo cite this article: Tiezhu Guo, Shungui Deng, Rene Schneider, Chuanfang Zhang& Jakob Heier (12 Dec 2025): Are MXenes viable as conductive, transparent filmsfor industrial applications?, Science and Technology of Advanced Materials, DOI:10.1080/14686996.2025.2597556To link to this article:  https://doi.org/10.1080/14686996.2025.2597556© 2025 The Author(s). Published by NationalInstitute for Materials Science in partnershipwith Taylor & Francis Group.Accepted author version posted online: 12Dec 2025.Submit your article to this journal Article views: 22View related articles View Crossmark dataFull Terms & Conditions of access and use can be found athttps://www.tandfonline.com/action/journalInformation?journalCode=tsta20https://www.tandfonline.com/journals/tsta20?src=pdfhttps://www.tandfonline.com/action/showCitFormats?doi=10.1080/14686996.2025.2597556https://doi.org/10.1080/14686996.2025.2597556https://www.tandfonline.com/action/authorSubmission?journalCode=tsta20&show=instructions&src=pdfhttps://www.tandfonline.com/action/authorSubmission?journalCode=tsta20&show=instructions&src=pdfhttps://www.tandfonline.com/doi/mlt/10.1080/14686996.2025.2597556?src=pdfhttps://www.tandfonline.com/doi/mlt/10.1080/14686996.2025.2597556?src=pdfhttp://crossmark.crossref.org/dialog/?doi=10.1080/14686996.2025.2597556&domain=pdf&date_stamp=12%20Dec%202025http://crossmark.crossref.org/dialog/?doi=10.1080/14686996.2025.2597556&domain=pdf&date_stamp=12%20Dec%202025https://www.tandfonline.com/action/journalInformation?journalCode=tsta20ACCEPTED MANUSCRIPT Publisher: Taylor & Francis & The Author(s). Published by National Institute for Materials Sci-ence in partnership with Taylor & Francis Group. Journal: Science and Technology of Advanced Materials DOI: 10.1080/14686996.2025.2597556 Are MXenes viable as conductive, transparent films for industrial applications? Tiezhu Guo1,2, Shungui Deng2, Rene Schneider2, Chuanfang Zhang2* and Jakob Heier 2* 1 Functional Nanomaterials, Catalonia Institute for Energy Research (IREC), Sant Adrià de Besòs, 08930 Barcelona, Spain 2 Laboratory for Functional Polymers, Empa, Swiss Federal Laboratories for Materials Science and Technology, Uberlandstrasse 129, CH-8600, Dübendorf, Switzerland  *Corresponding author ruoshuang123@gmail.com and Jakob.heier@empa.ch   Abstract Two-dimensional transition metal carbides and nitrides, so-called MXenes, hold significant promise as flexible transparent conductive electrodes (TCEs) in diverse applications. However, MXenes fall below the minimum requirements for industrial use, largely due to factors such as the quality of MXene flakes, electrical conductivity, optical conductivity, and transparent electrode fab-rication techniques. In this study, we analyze the relationships among nanosheet size, DC- and opti-cal conductivity and its ratio (σDC/σop), and sheet resistance (Rs) of MXene TCEs based on data from published literature. Compared to Ti3C2Tx TCEs fabricated with low-quality, small-sized flakes (< 1 μm, σDC/σop < 10), those made with high-quality, large-sized nanosheets (>6 μm) with narrow size distributions (σDC/σop > 20) exhibit dramatically reduced Rs by several orders of magni-tude while maintaining high transmittance. Nevertheless, the  σDC/σop of continuous Ti3C2Tx metal-lic TCEs saturates at ~24, fairly below the basic requirements for commercial TCEs. By integrating a metallic silver grid onto Ti3C2Tx TCEs, a remarkable σDC/σop ratio of 330 has achieved, bringing MXene TCEs closer to fulfilling industrial application standards and inspiring greater confidence in their future adoption. Beyond the field of TCEs, the insights gained here could inspire advance-ments in other areas, such as optoelectronic devices, flexible displays, and energy-efficient trans-parent technologies. This work provides a framework for the design and development of next-https://crossmark.crossref.org/dialog/?doi=10.1080/14686996.2025.2597556&domain=pdfACCEPTED MANUSCRIPT generation transparent conductive materials with broad implications across various scientific and industrial domains.  Keywords: transparent conductive electrodes, MXenes, figure of merit, percolation, theoretical lim-itation   ACCEPTED MANUSCRIPT Introduction Transparent conductive electrodes (TCEs) with high conductivity and transparency are essential for a wide range of applications, including transparent supercapacitors, antennas, electromagnetic shielding, and sensors, among others [1]. Traditionally, indium tin oxide (ITO) and fluorine-doped tin oxide (FTO) have served as the first generation of commercial TCEs, offering low sheet re-sistance (Rs, <10 Ω sq-1) and high transparency (T, >90%) in the visible range [1-4]. However, as ceramic materials, ITO and FTO are prone to cracking and fracturing under relatively low strains of 2~3% [5]. The expansion of microcracks further results in a sharp increase in resistance. This limi-tation has driven the development of flexible transparent electrodes as replacements for ITO in flex-ible electronics. Promising alternatives for flexible TCEs include transparent conductive films based on materials such as silver nanowires, carbon nanotubes (CNTs), PEDOT, graphene, and MXene, but also mesh-es fabricated from metals [3, 4, 6, 7]. The performance of TCEs is typically characterized by the re-lationship between transparency (T) and sheet resistance (Rs), as described by the following equa-tion:[8] T=(1+188.5RsσopσDC)-2        (1) where σop is optical conductivity, σDC  is DC conductivity, σDC/σop is defined as the figure of merit (FOMe), which is commonly used to evaluate the optoelectronic performance of TCEs. A higher FOMe indicates that films can be thinning down to the highly transparent region without dramatical-ly increasing its resistance. To replace fragile ITO in many applications, the minimum industrial standard must be met, which requires Rs < 100 Ω sq-1 at T > 90% in the visible range [1]. This cor-responds to a basic requirement of σDC/σop > 35, as derived from Equation 1 [1]. However, many cases demand Rs < 10 Ω sq-1 at T > 85%, implying that σDC/σop > 220 must be achieved [1]. We note that the upper limits of the optoelectronic properties of graphene-based TCEs have been discussed in previous studies, with maximum figure of merit (σDC/σop) values saturate at ~0.7 and 11 for liquid-exfoliated and CVD graphene flakes (without doping), respectively [8]. Clearly, these values fall significantly below the minimum industrial standards. MXene, a family of 2D transition metal carbides, nitrides, and carbonitrides, offers excellent conductivity and being highly transpar-ent when the thickness is several nanometers. Moreover, MXene is water-dispersible and can be processed into transparent conductive films at room temperature using methods such as blade coat-ing, slot-die coating, and spin coating [3, 4, 9]. Some Ti3C2Tx-based TCEs have demonstrated im-pressive optoelectronic performance, such as a sheet resistance of 222 Ω sq-1 with a transmittance of ACCEPTED MANUSCRIPT 92% [4]. However, these results remain insufficient to replace ITO or silver nanowires as TCE ma-terials.  We also note that to date, the true metrics for evaluating MXene-based transparent electrodes have yet to be established. For instance, most studies only report the transmittance (T) and sheet re-sistance (Rs) of the films, which are often inconsistent due to varying film thicknesses. This varia-bility makes direct comparisons between MXene-based films and other TCE materials difficult. At high transmittance (T > 90%), even slight changes in transparency can lead to a sharp increase in Rs, as the reduced thickness compromises conductive pathways within the electrode. Utilizing the fig-ure of merit (FOMe) to represent the optoelectronic properties relative to other conductive transpar-ent films remains the most straightforward parameter for comparison. Additionally, we recognize the importance of understanding the upper limit of FOMe in MXene TCEs, as it tells us the maxi-mum achievable value and the potential in practical applications. However, to date, no reports on the theoretical limitation of FOMe are available for MXene TCEs, to the best of our knowledge. In this work, we analyze the relationships between MXene nanosheet size, average conductivity, type of MXene (e.g., Ti3C2Tx, Ti2CTx, V2CTx, Ti3CNTx, etc.), figure of merit, optical conductivity, and sheet resistance in TCEs at high transparency. We identify the general trends and key factors affecting the optoelectronic performance of TCEs (e.g., the relationship between T and Rs), reveal-ing the potential maximum achievable FOMe fairly below the minimum industrial requirements. As such, we introduce a metallic Ag mesh onto the MXene TCEs, leading to significantly reduced Rs while marginally affecting T. The Ag mesh-MXene TCEs exhibits a record-high FOMe up to 330, positioning MXene as a strong candidate for use as a flexible transparent electrode in industrial ap-plications. Experiments Fabrication of MXene nanosheets: 0.8 g of LiF was added to 10 ml of 9 M HCl and stirred continuously in an oil bath at 35°C for 10 minutes. Then,  0.5 g of Ti3AlC2 was gradually added to the above solution. After 24 hours of reac-tion, the resulting precipitate was washed with deionized water and centrifuged at 1,500 rcf for 5 min until the supernatant became dark green and the pH approached ~6. Next, 100 ml of deionized water was added to the precipitate and manually shaked until the precipitate was completely re-dispersed. The solution was degased under argon for 10 min, then sonicated continuously in an ice bath for 60 min at 35 kHz. The dispersion was centrifuged at 1,500 rcf for 30 min and the upper suspension was collected to obtain Ti3C2Tx nanosheets. TCE fabrication  ACCEPTED MANUSCRIPT The silver meshes were printed through an aerosol jet printer (Optomec Decathlon AJ-5X) with a nozzle of size 100 μm using the Novacentrix JS-ADEV N250 silver nanoparticle ink on top of the MXene film. During the printing process the ink flow was kept constant, so that the variation of the printing speed (6, 9 and 12 mm/s) controls the printed line width and height, respectively. The uni-form Ti3C2Tx films were coated onto glass substrate using the slot-die coating method, with the fab-rication process and characterization details of the MXene nanosheets provided in our previous study [3]. After drying the ink at room temperature, the samples were annealed at 200°C on a hot plate under argon atmosphere for 2 hours.  Film Characterization  The topography of the printed meshes was obtained by confocal microscopy. The microscope (Leica DCM8) was equipped with a EPI-150X-L objective from Leica, which offers a resolution of 140 nm and 2 nm in x,y- and z-direction, respectively. The sheet resistance (Rs) of the Ag/MXene films was measured using a four-wire measurement method (Keithley 2400 SourceMeter) under ambient conditions. For the MXene films, measurements were conducted using a Jandel RM3-AR four-point probe, with the final value calculated as the average from 10 independent locations on sample. Optical transmittance spectra were recorded using a UV-vis spectrophotometer (Varian Cary 50) over the wavelength range of 350-800 nm. The transmittance at 550 nm, a commonly used reference wavelength for evaluating the transparency of thin films, was determined as the average of five measurements taken from randomly selected positions on each TCE sample. In this study, the FOMe of the Ag/MXene composites was obtained by fitting the datapoints to Equation 1. Discussion  Reported Data for Sheet Resistance and Transmittance The reported data for the T and Rs of MXene-based TCEs show a significant variation, ranging from high-conductivity to high-resistance films, especially in the high transparency (T > 80%) region. We conduct a comprehensive analysis of over 20 studies on MXene-based TCEs, including Ti3C2Tx, Ti2CTx, Ti3CNTx, focusing on Rs and T [2-4, 9, 10-19]. Data are extracted from these studies and plotted to show T as a function of Rs, as depicted in Figure 1. The results reveal that Rs varies by 2~3 orders of magnitude, from approximately 400 Ω sq-1 to around 40 KΩ sq-1, even within similar transparency ranges. This underscores the need to investigate the differences among various MXene-based TCEs and identify the key factors that limit their optoelectronic performance. Calculated Conductivity Ratio for Published Data We plotted the figure of merit (FOMe) values and MXene flake sizes from the same data set. For each system, we generally extract the average or highest value, as shown in Figure 2a. It is evident ACCEPTED MANUSCRIPT that there is a clear correlation between the FOMe of these TCEs and the flake sizes, larger MXene flakes exhibit superior optoelectronic properties compared to those of smaller ones. We define flake size of ~1 μm as the cutoff standard; flakes (several hundred nanometers) smaller than this are typi-cally produced through sonication. Interestingly, the graph can be divided into two sections, MXene films with flake sizes below 1 μm never show σDC/σop values larger than 10, while the FOMe value for MXene films with flake sizes larger than 1 μm tend to exceed 10 with ease. For instance, a max-imum FOMe of ~24 was achieved in Ti3C2Tx TCEs with flake size of ~7 μm. Among various types of MXene with similar flake sizes, Ti3C2Tx exhibits the highest FOMe compared to other MXene types, indicating that this type of MXene is the choice of option (Figure 2b) [9, 13, 17, 20, 21]. Therefore, Ti3C2Tx is selected as the representative material for further analysis of the optoelectron-ic properties of TCEs. We performed polynomial fitting (other fitting methods yielding more unre-alistic results) for the relationship between Ti3C2Tx flake sizes and FOMe (Figure 2c), as well as for the sizes of various types of MXenes and FOMe (Figure 2d). The coefficients of determination (R2) were 0.76 and 0.65, respectively. Although the R2 values are not particularly high, the fitted curves still capture the trends in the experimental data, and the model parameters are consistent with prac-tical relevance. This suggests that increasing flake size appears to be an effective and feasible ap-proach, particularly for undoped pure MXene.  We further analyze whether variations in σDC or σop are responsible for the wide range of FOMe values observed. Only a few reports provide the thickness of the TCEs, making it impossible to cal-culate σDC and σop in many cases. We extract available data and organized it in Figure 3a. The σop values vary randomly between 275 and 750 S cm-1, with a median value of 564 S cm-1. This varia-tion depends on the intrinsic characteristics of the material and the number of layers per unit volume. The optical conductivity differences of Ti3C2Tx TCEs are further analyzed, with σop values of 520, 675, 750, 275, 680 S cm-1 derived from blade coating, slot-die coating, spin coating, and inkjet printing, gravure printing, respectively [2-4, 18, 19]. Guo et al. demonstrated that TCEs fabricated using blade coating or slot-die coating technologies exhibit higher orientation compared to those produced by spin-coating, as observed in surface morphology [3, 4]. We speculate that the variation in  σop is due to morphological differences between the films, such as surface roughness, free vol-ume, and compactness. Although slight differences in σop between Ti3C2Tx and V2CTx (481 S cm-1)[20] are reported here, we consider this difference to fall within an acceptable fluctuation range due to the limited data available. However, the average DC conductivity (σDC) of the TCEs varies significantly, ranging from 3,092 to 15,000 S cm-1 (Figure 3b). This suggests that the variation in FOMe is primarily influenced by changes in σDC. ACCEPTED MANUSCRIPT In MXene TCEs, charge carriers migrate along the direction with the lowest energy barrier within a single flake, then overcome the interflake tunneling barriers to jump onto another flake. Therefore, the total resistance (Rtot) of the TCEs consists of in-plane resistance which represents the inherent resistance (Rinh) of the MXene flakes, and interflake resistance (Rint) which relates to the quantity of interflake junctions in the horizontal direction and intercalants in the vertical direction [22]. Here, the inherent resistance and the residual Li⁺ content are mainly determined by the etching and delam-ination process. Previous studies have shown that the LiF/HCl etching route results in fewer defects on individual flakes compared to HF etching [23], and reducing the residual Li⁺ between layers can improve conductivity [24]. In all cases, the delaminated MXene used for TCE preparation was ob-tained via conventional HF or LiF/HCl etching routes. Additionally, the significant difference in conductivity of Ti3C2Tx-based TCEs reflects variations in the number of interflake tunneling barriers. The number of these barriers depends on the flake sizes and the degree of aggregation or delamination. In films prepared from adequately delaminated, large-sized MXene flakes, there are relatively few interflake barriers. In contrast, as the flake sizes decrease, the number of boundaries significantly increases. This explains why the FOMe of large-sized MXene films appears in the upper region of Figure 2a, while the FOMe of small-sized films is found in the lower region. Thus, empirically, the FOMe of TCEs can be expressed as FOMe ∝ σDC, or FOMe ∝ Rtot-1= (Rinh +Rint)-1. Here, Rtot ≈ Rinh, when the flake size approaches infinity, meaning that σDC and FOMe values become dependent of the inherent conductivity. Consequently, to achieve the highest performance, we should prepare MXenes with few defects such as pinholes or mi-cropores in the in-plane flakes and smooth edges. Limiting values of σDC/σop The σDC and σDC/σop of TCEs are influenced by MXene types (intrinsic resistance), flake sizes, and the degree of delamination (interflake resistance). We anticipate that σDC can be maximized by fabricating large-sized, highly delaminated MXene flakes. In our previous work, we prepared pre-dominantly large-sized Ti3C2Tx flakes (12.2 μm) with a narrow size distribution [4]. Films from these flakes exhibit the highest FOMe of 29, with Rs=77 Ω sq-1 at T=83.4%. The TCE demonstrates a high σDC of 19,325 S cm-1, which, to our knowledge, is the highest reported value from conven-tional etching methods (HF or HCl/LiF) for Ti3AlC2. Unlike liquid-exfoliated graphene flakes, de-laminated MXene flakes are obtained by etching the as-received MAX phase using hydrofluoric (HF) or HCl/HF etching methods, or by in situ HF formation methods (such as LiF/HCl with or without intercalants). These methods pose challenges in obtaining large, delaminated Ti3C2Tx flakes (larger than 10 μm) with a broad size distribution due to the inherent limitations of the synthesis ACCEPTED MANUSCRIPT process. Gogotsi et al. have reported Ti3C2Tx with an average lateral size of 14 μm and a maximum size up to 40 μm, albeit in small quantities [25]. Notably, to meet the minimum industrial standard of FOMe >35, maximizing the conductivity of TCEs and minimizing interfacial resistance become critical. Assuming the use of ultralarge Ti3C2Tx flakes (up to 40 μm) to fabricate TCEs via the slot-die coating process (with an optical conductivity of 675 S cm-1), applying the formula FOMe = σDC/σop, it can be inferred that the DC conductivity of TCEs needs to exceed 23,625 S cm-1, which is evidently achievable. This inference is supported by two key findings, (1) MXene flakes with an average size of 12.2 μm have already achieved a maximum DC conductivity of approximately 20,000 S cm-1 [4], demonstrating the potential of larger flakes in reducing interflake resistance and enhancing conductivity. (2) Zeraati et al. reported achieving a DC conductivity of 24,000 S cm-1 us-ing Ti3C2Tx flakes with an average size of only 1.8 μm via the evaporated-nitrogen minimally inten-sive layer delamination (EN-MILD) method [26]. We believe that preparing large-sized Ti3C2Tx flakes through the EN-MILD method will significantly reduce interflake resistance, which could lead to enhanced DC conductivity and improved σDC/σop values, thus enabling superior performance in TCEs applications. Surpassing limits through integration with metal mesh Obviously, the pure MXene TCEs based on continuous metallic films give a practical maximum FOMe of 24, which falls short of the required standard for advanced optoelectronic devices such as the touch panels. Unless ultralarge MXene nanosheets are prepared using special, complex process-es as described above (which typically have low yield), this approach, although theoretically feasi-ble, faces significant challenges in practical implementation. To beat the practical limitations, one should revolutionize the TCE architecture by replacing continuous films with mesh structures to substantially improve T without affecting Rs. As such, advanced TCEs can be fabricated using con-ventional small MXene nanosheets. This is especially true when the mesh is rationally designed, al-lowing more light to pass through instead of absorbed by the MXene flakes, leading to much in-creased T. Unfortunately, creating MXene mesh on substrates inevitably decreases the uniformity of corresponding TCEs. To counter such a negative effect, depositing metal grids onto the uniform MXene film to create a metal grid/MXene structure should result in much lower Rs at much higher T, along with uniform electrical, optical and thermal conductivity. As such, we break the FOMe limita-tion of MXene TCEs by fabricating metal grid/MXene hybrid TCEs, making them a promising al-ternative to fragile ITO in applications.  The Ag grids/Ti3C2Tx (Ag/MX) hybrid TCEs were accomplished by digitally controlled aerosol jet printing of Ag ink onto dried Ti3C2Tx TCEs. The XRD patterns and size distribution of the Ti3C2Tx  flakes are shown in Figures 4a, b, c, with the flake size being approximately 1 µm. Here, ACCEPTED MANUSCRIPT these uniform Ti3C2Tx films were deposited onto a glass substrate using the slot-die coating tech-nique, with the details provided in our previous work [3]. The hybrid TCEs were manufactured with an area of 5 × 5 cm², featuring a line pitch of 1 mm in both vertical and horizontal directions, sche-matics shown in Figure 4d. To control the width and height of the Ag lines, we adjusted the print-ing speed, resulting in three hybrid TCEs variants with average Ag line dimensions of 26.2/0.839 μm, 15.4/0.497 μm, and 14/0.298 μm for width/height, respectively. These variants are labeled as Ag-1/MX, Ag-2/MX, and Ag-3/MX (Figures 4e, 4f, 4g). The Ag-1, Ag-2, and Ag-3 grids demon-strated high transparency of 96.4%, 97.5%, and 97.4%, with corresponding sheet resistances of 3.1, 4.6, and 15.8 Ω sq-1, respectively. When these Ag-1, Ag-2, and Ag-3 grids were deposited onto Ti3C2Tx TCEs (T = 89%), the transparency of the hybrid TCEs decreased to 82.1%, 83.5%, and 84.7%, with corresponding sheet resistances of 5.6, 9.2, and 21.9 Ω sq-1, respectively (Figure 4h). This indicates that the transmittance of the hybrid TCEs primarily depends on the Ti3C2Tx TCE at the same line pitch of the Ag grid. As shown in Figure 4i, the FOMe values for Ag-1/MX, Ag-2/MX, and Ag-3/MX were 100, 220, and 330, respectively, representing a significant improvement compared to pure continuous MXene TCEs. To meet the requirements of industrial applications for TCEs that are made from small-sized MXene nanosheets produced using conventional synthesis methods, without relying on strict processes to produce high-quality large-sized MXene nanosheets (which typically have low yield), depositing Ag or other metal mesh structures onto MXenes for hybrid TCE fabrication is a promising design strategy, which could enable MXenes to replace ITO in the future. Conclusion In this work, we analyzed both the potential of MXene-based transparent conductive electrodes (TCEs) for industrial applications and their theoretical limitations of FOMe, while also developing hybrid Ag-grid/MXene TCEs to overcome these challenges. While pure MXene continuous films show promising conductivity and transparency, their figure of merit (FOMe) saturates at around 29, which is far below the minimum industrial requirement of 35. The limitations of MXene-based transparent conductive electrodes (TCEs) arise from the inherent properties of MXene flakes, such as their type, size, yield, and challenges in achieving high electrical conductivity and low optical conductivity. These factors lead to insufficient technical specifications and pose challenges for large-scale production. Here, key challenges include the difficulty in obtaining large, defect-free flakes and the inability to achieve the required balance of conductivity and transparency. Hybridiz-ing MXene with metal mesh structures is the future for TCEs, as this strategy significantly im-proves the FOMe, providing a scalable solution to meet industrial standards and enabling MXene-based TCEs to replace ITO in practical applications. ACCEPTED MANUSCRIPT Acknowledgements We acknowledge funding from the SFA-AM project grant for SCALAR by the ETH Board. Conflict of Interest  The authors declare no conflict of interest. References 1. Zhang C, Nicolosi V. Graphene and MXene-based transparent conductive electrodes and supercapacitors. Energy Storage Mater. 2019;16:102-125. doi: 10.1016/j.ensm.2018.05.003. 2. Zhang C, Anasori B, Seral-Ascaso A, et al. Transparent, Flexible, and Conductive 2D Titanium Carbide (MXene) Films with High Volumetric Capacitance. Adv. Mater. 2017;29(36):1702678. doi: 10.1002/adma.201702678. 3. Guo T, Zhou D, Gao M, et al. Large-Area Smooth Conductive Films Enabled by Scalable Slot-Die Coating of Ti3C2Tx MXene Aqueous Inks. Adv. Funct. 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Transmittance (T) and sheet resistance (Rs) data from literature reports [2-4, 9-19]. Data are divided into 3 categories (MXene flake sizes of < 1μm, 1-5 μm, > 5 μm). The black star is the lowest industrial standard value for transparent electrodes.  ACCEPTED MANUSCRIPT Figure 2.ues are emerit (FOflake sizMXene d  . (a) FOMe extracted or OMe) of difes from Tidatasets.  values of vfitted fromfferent-typei3C2Tx datasarious MXem T and Rs de MXene at set. (d) Fittenes as a fudata reportedt similar flating curve unction of fld in the liteake sizes. (cof FOMe vlake sizes. Terature. (b) Cc) Fitting cuvalue and flThe FOMe (Comparisonurve of FOMflake sizes  (σDC/σop) van of figure Me value anfrom varioual-of nd us ACCEPTED MANUSCRIPT Figu ure 3. The opptical conduuctivity (a) and DC connductivity (bb) extractedd from the l iterature. ACCEPTED MANUSCRIPT Figure 4.spectivellines undSheet resflakes sizgrid/MX The black . (a, b, c) XRly. (d) Schemder printingsistance anze is about hybrid TCk star is theRD patternsme of the pg speed 6, 9nd transmitt1 μm. Ag Es betweene lowest indu s, SEM imarinted grids9, 12 mm stance of Ti3grid was prn T with Rs,ustrial standage, and pars on the MXs-1, respectiv3C2Tx, Ag rinted onto , also includdard value frticle size diXene TCE. (vely. Left sgrid and Athe Ti3C2Tded are fittifor transparistribution o(e, f, g) Theside: width,Ag-grid/MXTx TCE. (i) ng curves aent electrodof the Ti3C2e width and , Right sideX hybrid TCThe relatioaccording todes. 2Tx flakes, rheight of Ae: height. (hCEs. Ti3C2Tonship of Ago Equation  re-Ag h) Tx g-1. ACCEPTED MANUSCRIPT  GraphicalAbstract1    ACCEPTED MANUSCRIPT Impact Statement A coated MXene film alone cannot meet industrial standards for transparent conductive electrodes; however, when integrated with a printed silver grid, it successfully achieves the required transpar-ency and conductivity levels.