Silver Nanowires and Silanes in Hybrid Functionalization of Aramid Fabrics

New functionalization methods of meta- and para-aramid fabrics with silver nanowires (AgNWs) and two silanes (3-aminopropyltriethoxysilane (APTES)) and diethoxydimethylsilane (DEDMS) were developed: a one-step method (mixture) with AgNWs dispersed in the silane mixture and a two-step method (layer-by-layer) in which the silanes mixture was applied to the previously deposited AgNWs layer. The fabrics were pre-treated in a low-pressure air radio frequency (RF) plasma and subsequently coated with polydopamine. The modified fabrics acquired hydrophobic properties (contact angle ΘW of 112–125°). The surface free energy for both modified fabrics was approximately 29 mJ/m2, while for reference, meta- and para-aramid fabrics have a free energy of 53 mJ/m2 and 40 mJ/m2, respectively. The electrical surface resistance (Rs) was on the order of 102 Ω and 104 Ω for the two-step and one-step method, respectively. The electrical volume resistance (Rv) for both modified fabrics was on the order of 102 Ω. After UV irradiation, the Rs did not change for the two-step method, and for the one-step method, it increased to the order of 1010 Ω. The specific strength values were higher by 71% and 63% for the meta-aramid fabric and by 102% and 110% for the para-aramid fabric for the two-step and one-step method, respectively, compared to the unmodified fabrics after UV radiation.


Introduction
Due to their low density, high tensile strength, excellent thermal stability, high specific strength, and modulus of elasticity, aramid fibers are widely used in special clothes accessories and technical products [1]. Their weakness, however, is their poor resistance to UV radiation. Aramids absorb UV radiation in the range of 300 to 400 nm, which results in breaking of the intermolecular bonds in the polymer that causes deterioration of the mechanical properties [2,3]. Therefore, it is important to protect them against UV radiation such as by modification with nanosilver, which also provides antibacterial and antistatic properties. Such functionalization significantly extends the scope of their application, such as materials for thermal sensors in smart clothes, for the protection of electronic communication, and in aviation [4][5][6]. The molecular structure of aramid fibers, which consist of aromatic rings and amide groups, makes them highly crystalline [7,8]. Due to the smooth and chemically inert surface, they show poor adhesion to modifiers. In order to improve the functionalization efficiency, an initial surface modification is performed through plasma activation and deposition of a polydopamine thin film by oxidative polymerization of dopamine [9]. The activation increases the free surface energy of aramid fibers and creates aramid fabrics, which can be used in many fields, e.g., in the automotive and military industry, in protective clothing in high-risk occupations, to monitor vital functions or the level of available oxygen, and also in everyday life as textile materials for tents, umbrellas, and covering fabrics, etc.
The synthesis was performed in a Radleys 1l Reactor-Ready (Radleys, Essex, United Kingdom) reactor equipped with a mechanical stirrer, working at a speed of 150 RPM. The reactor has a double heating jacket, allowing for precise temperature control performed by an external thermostat during the entire synthesis. The temperature was set at 170 ± 2 • C.
A total of 600 mL of ethylene glycol, 30 g of PVP, and 0.42 g of sodium chloride (NaCl, CHEMPUR, PiekaryŚląskie, Poland) were heated to 167 • C (constant temperature control) and stirred at 150 RPM to obtain a homogenous solution. Then, a mixture of 6.12 g of AgNO 3 in 300 mL of ethylene glycol was added with a peristaltic pump at a rate of 3.33 mL/min for 90 min into the heated solution of ethylene glycol, PVP, and NaCl. When the silver precursor solution was added, the colloid was stirred at 150 RPM and heated for 60 min at 167 • C.
After the synthesis, the solution was air-cooled to about 25 • C. To remove ethylene glycol and excess PVP from the colloid, the subsequent, small parts of the solution were diluted with acetone (C 3 H 6 O, 99,5%, Avantor, Gliwice, Poland) with a ratio of 1:10 and shaken for 10 min. Then, the silver nanowires were dispersed in anhydrous ethyl alcohol (C 2 H 6 O, 99,8%, Avantor, Gliwice, Poland). The obtained AgNWs colloid concentration was 4000 ppm, the length of the AgNWs was about 10 ± 2 µm, and the diameter was about 42 ± 3 nm.

Low-Pressure Air RF Plasma Treatment of Aramid Fabrics
Para-aramid and meta-aramid fabrics were washed in diethyl ether for 30 min and dried at 25 • C. Next, both fabrics were treated with a low-pressure air RF plasma (Zepto plasma system, Model 2. Diener Electronic, Ebhausen, Germany) for 10 min. The pressure in the plasma chamber was set at 0.3 mbar with laboratory air (Linde Gaz, Kraków, Poland) with the purity: 20% of O 2 and 80% of N 2 (40% relative humidity) as the working gas. The power of the plasma was set at 50 W and the generator frequencies was 40 kHz.

Polydopamine Functionalization of Aramid Fabrics
A dopamine solution with a concentration of 2 g/L was prepared by dissolving dopamine hydrochloride (Sigma Aldrich, UK) in distilled water. The pH of the solution was adjusted to 8.3 by adding tris/glicyne buffer (BIO RAD, Warszawa, Poland). The plasma treated aramid fabrics were immersed in the dopamine solution for 24 h (Figure 1a). Under the same conditions, a polydopamine coating was prepared on the surface of the aluminum plate. This material was used for the acquisition of a reference FTIR spectrum of pure polydopamine. After that, all samples were rinsed with distilled water three times and then dried for 24 h at 25 • C. Silanes Sol Preparation APTES (Unisil, Tarnów, Poland) and DEDMS (Sigma Aldrich, Gillingham, United Kingdom) differ in their chemical structure, brittleness, and hydrophobicity. To prepare the AgNWs and silane modified aramid fabrics, silanes sol was prepared by mixing 15.00 g of APTES, 1.12 g of DEDMS, and 3.93 g of 1 M HCl (Avantor, Gliwice, Poland). The silanes mixture was shaken for 30 min. Next, ethyl alcohol (C 2 H 6 O, 99.8%, Avantor, Gliwice, Poland) was added at 50% by volume of the silanes mixture.

AgNWs and Silanes Functionalization of Aramid Fabrics
The one-step (mixture) and two-step (layer-by-layer) methods were used for the functionalization of aramid fabrics with AgNWs and silanes (Figure 1b). In the one-step method, aramid fabrics were 5-fold dipped in a mixture of a AgNWs colloid (Ag) with 10 wt.% silanes sol (S) for 1 min. After the mixture was applied every time, the fabrics were dried in an oven at 100 • C for 1 h. The fabrics modified with the mixture (Ag + S) are denoted as mAr/RF/PD/5Ag+S and pAr/RF/PD/5Ag+S for the metaand para-aramid fabric, respectively.
In the two-step method, fabrics were dipped in the AgNWs colloid for 1 min and dried at 25 • C. The AgNWs colloid (Ag) was applied 5 times. Then, the fabrics were dipped 1 time in the silanes sol (S) and then dried in an oven at 100 • C for 1 h. The fabrics modified with the layer-by-layer (Ag/S) method are denoted as mAr/RF/PD/5Ag/S and pAr/RF/PD/5Ag/S for the metaand para-aramid fabric, respectively.
In Table 1, the values of mass per unit area of the reference and functionalized aramid fabrics are summarized.

UV Irradiation
The UV irradiated unmodified and modified fabrics were placed between two (100 W) LED diodes with the maximum wavelength of the emitted light at 365 nm for 96 h. The irradiance (W) was determined by using the CUV 4 irradiance sensor (Kipp & Zonen B.V., Delft, Netherlands) to measure the intensity of the light in the UV range (305-385 nm). The supplied irradiation energy (P) was calculated from Equation (1) [37] and determined to be 46,719 kJ/m 2 for one LED diode.
where P is the irradiation energy (kJ/m 2 ), t is the irradiation time (h), W is the irradiance (W/m 2 ), and n is the number of measurements during the irradiation time t.

Characterization Methods SEM/EDS Analysis
The morphology and chemical composition analysis were performed using a scanning electron microscope (SEM) (Nova NanoSEM 450 FEI, Hillsboro, OR, USA) and VEGA 3 (TESCAN, Brno, Czech Republic) with an energy dispersive spectroscopy (EDS) X-ray microanalyzer INCA Energy (Oxford Instruments Analytical, High Wycombe, United Kingdom) with a magnification of 2500×, 10,000×, and 20,000×. A total of three EDS spectra were recorded for each sample, and mean values of the weight percentage of the elements were determined.

Optical Microscopy
The images of the fabric surface before and after the abrasion process were acquired using an optical microscope DSX1000 (OLYMPUS, Tokyo, Japan) and using the DEPH function to increase the depth of field. A magnification of 300× was used for all images.

FTIR Analysis
FTIR/ATR (Fourier transform infrared spectroscopy/attenuated total reflectance) spectra of reference and plasma-treated yarns were recorded in the range 600-4000 cm −1 using Nicolet IS 50 spectrometer (Thermo Fisher Scientific Inc., Bartlesville, OK, USA) with GATR (grazing angle attenuated total reflectance) accessory (Harrick Scientific Products Inc., New York, NY, USA) using the MCT (mercury-cadmium-telluride) detector. This accessory allows to collecting spectra from the surface of the fibers at a depth of about up to 50 nm.

Surface Properties
The analysis of the surface properties of the fabrics was performed by the goniometric method using the goniometer PGX (Fibro System AB, Stockholm, Sweden). In order to determine the surface free energy (γ s ), three standard liquids with known surface tensions and different values of dispersive and polar components were applied ( Table 2). The drop of liquid with a volume of 4 µL was applied. A total of three repetitions for each sample were used. The surface free energy was determined according to the Wu model (Equation (2)), which is based on the assumptions of the Owens-Wendt model [7,[38][39][40][41][42] but describes the intermolecular interaction using the harmonic mean.
where γ s d and γ s p are the dispersive and polar components of a solid, respectively, and γ l d and γ l p are the dispersive and polar components of a liquid, respectively.

Specific Strength
The study of the specific strength of the fabrics before and after UV irradiation was performed by using the Instron 3367 Test Machine (United Kingdom) in accordance with PN-EN ISO 13934-1:2013-07 Textiles-Tensile properties of flat products-Part 1: Determination of maximum force and relative elongation at maximum force by the strip method. A total of five repetitions for each sample were used. Samples were conditioned for 24 h at a temperature of 21.0 ± 1.0 • C and a relative humidity (RH) of 64.4 ± 0.1% and then tested in the same conditions.

Abrasion Resistance
The resistance to abrasion of the fabrics before and after UV irradiation was studied using the Martindale unit (United Kingdom) in accordance with PN-EN ISO 12947-2:2017-02 Textiles-Determination of the abrasion resistance of fabrics by Martindale method-Part 2: Determination of specimen breakdown. A total of three repetitions for each sample were used. Samples were conditioned for 24 h at a temperature of 21.1 ± 0.1 • C and an RH of 64.4 ± 0.1% and were tested in the same conditions. A standard woolen fabric was used as an abrasive cloth. An abrasive load of 12 kPa was applied.

Conductivity
The electrical surface resistance (R s ) and electrical volume resistance (R v ) of the fabrics before and after UV irradiation were determined according to the PN-EN 1149-1:2008 for R s and PN-EN 1149-2:1999+A1:2001 for R v , using a set of standard electrodes and a 6206 teraohmmeter (ELTEX, Weil am Rhein, Germany). The fabrics were conditioned for 24 h in the HCZ 0030 L(M) chamber (Heraeus, Hanau, Germany) at a temperature of 23.0 ± 2.0 • C and an RH of 25.0 ± 5.0% and were tested in the same conditions.

Modification of the Aramid Fabrics with Low-Pressure Air RF Plasma and Polydopamine
The surface of the meta-( Figure 2a) and para-aramid ( Figure 2a) fibers is smooth with visible longitudinal cracks. Aramid fibers have a fibrillar structure. Activation in low-pressure RF plasma causes an increase in the unevenness and surface roughness (Figures 1b and 2b). The dopamine solution prepared for the functionalization of the plasma-activated aramid fabrics was colorless and transparent. During the oxidative autopolymerization of dopamine, the color of the solution quickly turned pink as catechol was oxidized to benzoquinone. Then, the pink solution slowly turned to dark brown. This indicates that after polymerization, the reaction of melanin formation takes place, resulting in the creation of polydopamine (PD) with a high strength of irreversible covalent bonds on the matrix. After modification, polydopamine formed a layer on the surface of both types of fibers (Figures 2c and 3c). The presence of the polydopamine coating on the aramid fiber surface was observed during the SEM analysis and confirmed by the FTIR spectroscopy results (Figure 4). In Table 3, the characteristic bands and their wavenumbers for the pAr fabric and polydopamine are presented. After application of the dopamine coating on the pAr fabric, an increase in the band intensity at 698 cm −1 , corresponding to the C-H bond out-ofplane of the substituted aromatic ring, and at 1513 cm −1 , corresponding to the C=N bond stretching vibrations of the aromatic ring, in relation to the unmodified pAr (Figure 3a) is observed. In the spectrum for the pAr/RF/PD fabric, bands are present in the spectrum for polydopamine but not in the spectrum for the reference pAr fabric. These are the bands at 911 cm −1 characteristic of the bending vibrations of the CONH bond and CN stretching, at 1440 cm −1 corresponding to the stretching vibrations of the C=C bond of the aromatic ring (Figure 4a), and at 3175 cm −1 corresponding to the stretching vibrations of the N-H bond (Figure 4b).

AgNWs and Silanes Modified Aramid Fabrics before and after UV Irradiation
SEM analysis shows that the surface of both aramid fibers after the 1-fold application of AgNWs (mAr/RF/PD/1Ag and pAr/RF/PD/1Ag) is covered unevenly (Figures 5a and 6a). After the 5-fold application, the coating is uniform (Figure 4b), with few areas without AgNWs (Figure 6b). AgNWs are found both on the surface of the fibers and inside the fabric structure. After application of the Ag+S mixture (Figures 5c and 6c), the AgNWs were embedded inside the silanes coating and deposited both on the surface of the fibers and in the spaces between them. In the case of the layer-by-layer method (Figures 5d and 6d), a layer of silanes covers the surface of the fabric with AgNWs. There are also fibers with AgNWs that protrude above the silanes surface.   (Table 4). For the mAr fabric, the content of C, N, and O is 68, 11, and 20 wt.%, respectively. For the mAr/RF/PD/1Ag fabric, the content of Ag is 3 wt.%, and for mAr/RF/PD/5Ag, it is 6-fold higher (Table 4). With the increase in the multiplicity of the AgNWs application, the content of C, N, and O decreased, which proves the effective coverage of the aramid fibers with AgNWs. For mAr/RF/PD/5Ag+S, the C and N content does not change significantly, and the O content, which is derived from the ethoxyl groups in silanes, increases by about 50% compared to mAr/RF/PD/5Ag. A decrease in the C content by 26% and an increase in the O and N content by 70% and 24%, respectively, are noted for mAr/RF/PD/5Ag/S in relation to mAr/RF/PD/5Ag. These changes are due to the presence of the silanes layer, which contains ethoxy groups and an amino group. The Ag content on the fiber surface is about 60% and 30% lower for mAr/RF/PD/5Ag+S and mAr/RF/PD/5Ag/S compared with mAr/RF/PD/5Ag. The Si content is 5 wt.% and 7 wt.% for mAr/RF/PD/5Ag+S and mAr/RF/PD/5Ag/S, respectively.
After 96 h of UV irradiation of the unmodified mAr ( Figure 7a) and pAr (Figure 8a) fabrics, the roughness of the fibers surface increased, and polymer fragments were present on the surface. The UV irradiation caused degradation of the AgNWs on the fabrics, as evidenced by silver precipitates on their surface (Figure 7b insert, Figure 8b insert). The coating on the mAr and pAr fibers modified with the Ag + S mixture was cracked (Figures 7c and 8c), and coating defects were visible, which proves that fragments of the Ag + S coating were detached (Figure 7c). UV radiation causes breaking of the polysiloxane bonds and photo-oxidation, which induces the formation of silanol and carbonyl groups [27]. In the case of the layer-by-layer method, the AgNWs did not degrade and did not change their morphology (Figures 7d and 8d). In the mixture method, the AgNWs were more exposed to the UV radiation due to the thin coating of silanes compared with the layer-bylayer method. This may cause the degradation of AgNWs and damages in silanes coating.   Table 5 presents the values of contact angles for water (Θ W ), formamide (Θ F ), and diiodomethane (Θ DIM ) for the unmodified and modified fabrics. Table 5. Contact angles of water (Θ W ), formamide (Θ F ), and diiodomethane (Θ DIM ) for unmodified and modified mAr and pAr fabrics.

Fabric Contact Angle [ o ]
Θ W Θ F Θ DIM mAr 64 ± 2 58 ± 2 63 ± 2 mAr/RF 19 ± 3 36 ± 3 27 ± 3 mAr/RF/PD 0 ± 0 36 ± 1 90 ± 0 mAr/RF/PD/1Ag 77 ± 2 74 ± 3 36 ± 4 mAr/RF/PD/5Ag 87 ± 1 90 ± 2 32 ± 3 mAr/RF/PD/5Ag+S 125 ± 5 106 ± 2 55 ± 2 mAr/RF/PD/5Ag/S 112 ± 2 96 ± 2 51 ± 1 pAr 77 ± 4 33 ± 2 14 ± 3 pAr/RF 12 ± 5 18 ± 5 5 ± 1 pAr/RF/PD 0 ± 0 19 ± 1 68 ± 1 pAr/RF/PD/1Ag 84 ± 4 77 ± 2 36 ± 3 pAr/RF/PD/5Ag 89 ± 3 85 ± 2 34 ± 4 pAr/RF/PD/5Ag+S 120 ± 1 106 ± 3 58 ± 2 pAr/RF/PD/5Ag/S 114 ± 2 100 ± 1 53 ± 1 For the mAr fabric, the Θ W value is 64 • , and after plasma activation, it decreases by 70%. For the pAr fabric, the Θ W value is 20% higher than for the mAr fabric. Plasma treatment reduced the Θ W value by 84%. The decrease in the Θ W value of pAr/RF is greater than for mAr/RF because of the chemical structure of both aramids and the higher degree of crystallinity of para-aramid, whose structure is more rigid and orderly, which causes greater changes on the fibers surface as a result of plasma etching [7]. After the application of the polydopamine coating, for the mAr/RF/PD and pAr/RF/PD fabrics, the value of Θ W is 0 • . The decrease in the Θ W value is due to the presence of active polar functional groups on the surface, such as -OH, -NH 2 , or -NH (Figure 4), which interact with the polar liquid. A decrease in the Θ W value was also observed by Sabdin et al. [42], who modified polypropylene (PP) meshes by immersing them in 10 mM dopamine buffered with TRIS at pH 8.5 for 24 h. Then, the PP meshes were washed several times with distilled water and dried at 40 • C. The Θ W value decreased from 138.9 • to 74.1 • . Jiang et al. [43] immersed a PP membrane for 24 h in a 1.0 g/L aqueous dopamine solution prepared by dissolving 0.25 g of dopamine in 250 mL of deionized water. Then, 1 mL of 1 M NaOH was added to the solution to adjust the pH to 9. The Θ W value decreased from 117.5 • to 54.3 • . Chen et al. [44] observed a decrease in the Θ W value from 143.7 • to 134.2 • after modification of the PP nonwoven fabric in an aqueous solution of dopamine hydrochloride at a concentration of 2 g/L and buffered with TRIS (pH = 8.5) for 24 h at 60 • C and then the samples were washed four times with ultrasounds and dried in a vacuum at 60 • C. This indicates the exposure of hydroxyl and amine groups in polydopamine on the nonwoven surface, which causes the increase in the wettability.
The Θ W values for both aramid fabrics with AgNWs are comparable and higher than for the unmodified fabrics, and their hydrophobicity increases with the increasing number of AgNWs deposited.
Fabrics modified with the mixture and layer-by-layer methods are hydrophobic. The mAr/RF/PD/5Ag+S and pAr/RF/PD/5Ag+S fabrics have the highest Θ W values, which are 125 • and 120 • , respectively. For the mAr/RF/PD/5Ag/S and pAr/RF/PD/5Ag/S fabrics, the Θ W values are 112 • and 114 • , respectively. Zeng et al. [31] reported that the water contact angle of the APTES film is 52 • , which means that APTES is hydrophilic. In turn, Zhang et al. [32] measured the contact angle of a DEDMS/TEOS silica aerogel (ratio of 0.26), which was 139.9 • , while TEOS is hydrophilic [45].
The value of the surface free energy (γ s ) for the mAr fabric is 39.8 mJ/m 2 , which is lower than for the pAr fabric by about 35% (Figure 9a,b). Plasma treatment and modification with polydopamine resulted in a significant increase in the γ s values by about 68% and 84%, respectively, for mAr and by about 87% and 83% for pAr fabrics in relation to the unmodified fabrics. After the 1-and 5-fold AgNWs application, the γ s value slightly decreased with the increase in the modification multiplicity for both types of aramid fabrics and is slightly lower in relation to the unmodified fabrics. The γ s values for the aramid fabrics modified with silanes by both methods are a little lower than for the fabrics after the 5-fold AgNWs application.
The dispersion component value (γ s d ) of the mAr fabric is 23.8 mJ/m 2 , which is lower than that of the pAr fabric by about 50%. The plasma treatment causes a 52% increase and 21% decrease in the γ s d component for the mAr/RF and pAr/RF fabric, respectively. The decrease in γ s d for the pAr fabric after plasma treatment in comparison with the mAr fabric is related to the higher degree of crystallinity and the fibrillization phenomenon of the reference pAr fabric (Figure 3a). For mAr fabric surface, the enlargement of the surface roughness is observed after plasma treatment (Figure 2b (Figures 2c and 3c). For both fabrics, after the 1-fold AgNWs application, the γ s d values are comparable. The lower γ s d value for pAr/RF/PD/1Ag compared with the reference fabric is caused by the fibrillization process, which significantly affects the dispersion component value. For the 5-fold AgNWs modified fabrics, the γ s d values are still comparable and lower than for the 1-fold AgNWs modification, which may be related to the smoothing of the discontinuous surface after successive AgNWs applications. For both aramid fabrics modified with silanes by the mixture and layer-by-layer method, the γ s d values are lower in relation to the fabrics after the 5-fold AgNWs application. Slightly higher γ s d values are found for the layer-by-layer method, which may be because of the visible AgNWs coated fibers that protrude above the smooth silane surface. The value of γ s p for mAr is 16.0 mJ/m 2 , which is six times higher than the value for pAr. After plasma treatment, the γ s p values increase and are comparable for both fabrics. The polydopamine application causes a further increase in the γ s p values by a factor of 2 and 1.7 for mAr/RF/PD and pAr/RF/PD, respectively. For fabrics modified with silanes by both methods, the γ s p values are lower compared to the unmodified fabrics. The values of the polar components are higher than the dispersive component values only for the fabrics modified with polydopamine. Unmodified fabrics have a smooth surface with numerous longitudinal cracks and fibrils. The surface is chemically inert, and there are no active functional groups. After application of polydopamine, an increase in γ s p in relation to γ s d is caused by an increase in the polarity of the polydopamine surface due to the presence of active functional groups on the fiber surface: -OH, -NH 2 , or -NH (Figure 4).

Specific Strength
The specific strength of the mAr fabric (8.6 N/tex) (Figure 10a) is 4.5 times lower than that of the pAr fabric, which does not change for mAr/RF/PD/5Ag and mAr/RF/PD/5Ag/S. For mAr/RF/PD/5Ag+S, the specific strength is higher than for the mAr fabric by about 12%. In the case of the modified pAr fabrics, a decrease by about 19%, 14%, and 17% is observed for pAr/RF/PD/5Ag, pAr/RF/PD/5Ag+S, and pAr/RF/PD/5Ag/S, respectively, compared to the unmodified fabric. The higher specific strength values after the application of the Ag+S mixture compared with the AgNWs modified fabrics are probably due to the stronger cross-linking of AgNWs with silanes, which occurred both on the surface of the fabric fibers and in the spaces between the fibers. For the layer-by-layer method, the cross-linking between the AgNWs and the silanes layer takes place only on the surface. The layer-bylayer modification does not change the specific strength of the fabrics in relation to the fabrics with AgNWs. After 96 h of UV irradiation, an almost 50% decrease in the specific strength is observed for the mAr fabric (Figure 10a). The specific strength is higher by 40%, 71%, and 63% for mAr/RF/PD/5Ag, mAr/RF/PD/5Ag+S, and mAr/RF/PD/5Ag/S, respectively, compared with the mAr fabric after UV irradiation. For the unmodified pAr fabric, there is a 60% decrease in the specific strength. For pAr/RF/PD/5Ag, pAr/RF/PD/5Ag+S, and pAr/RF/PD/5Ag/S (Figure 10b), their specific strength values are 58%, 102%, and 111% higher than for the UV irradiated pAr fabric, respectively. The significantly higher specific strength values after the AgNWs and silanes mixture and layer-by-layer modification is related to the reflection of UV radiation by silanes, which protects the AgNWs and aramid from UV degradation. Shi et al. [28] also observed the effect of the silane layer on the reflectance of UV radiation for a cotton fabric modified with graphene oxide and a KH570 silane layer. Tragoonwichian et al. [29] modified a cotton fabric using vinyletriethoxysilane, which significantly reduced the transmittance of UV radiation through the fabric.

Abrasion Resistance
The mAr fabric is abrasion resistant. After 100,000 cycles (Figure 11a), no breakage of the threads is observed ( Figure S1a, Supplementary Materials). For the pAr fabric, thread abrasion ( Figure S1b, Supplementary Materials) occurs after 5000 cycles (Figure 11b), probably due to the less ordered structure and lower degree of crystallinity of mAr than of pAr. For the mAr/RF/PD/5Ag and mAr/RF/PD/5Ag+S fabric, a decrease in the number of abrasion cycles by 40,000 compared to the mAr fabric is observed, which proves that AgNWs reduce the abrasion resistance of meta-aramid. In the case of the para-aramid fabrics, the application of AgNWs and a mixture of AgNWs and silanes improves the abrasion resistance and increases the number of abrasion cycles (Figure 11b) by 7000 and 75,000, respectively. For the layer-by-layer method, no thread damage is observed for both fabrics after 100,000 abrasion cycles. After UV exposure, the abrasion resistance of the mAr fabric decreased, the breakage of the threads is observed ( Figure S1a, Supplementary Materials), and the number of abrasion cycles decreases by a factor of seven. For the mAr/RF/PD/5Ag and mAr/RF/PD/5Ag+S fabric, the number of abrasion cycles is three times higher than that of the mAr fabric after UV irradiation. For the pAr fabric, the number of abrasion cycles does not change after UV exposure. For the modified fabrics, it is almost four times and 18 times higher for pAr/RF/PD/5Ag and pAr/RF/PD/5Ag+S, respectively, compared to the UV irradiated pAr fabrics. For the layer-by-layer method, after UV irradiation, no breakage of the fibers is observed after 100,000 cycles for both types of aramids, as before UV exposure ( Figure S1b, Supplementary Materials).

Conductive Properties
The unmodified mAr and pAr fabrics are non-conductive, and their electrical surface resistance (R s ) is 1.30 × 10 12 Ω and 1.26 × 10 12 Ω (Figure 12a), respectively. For both aramid fabrics after the 5-fold AgNWs application, a significant decrease in R s values by 10 orders of magnitude is observed. For both aramid fabrics modified with silanes by the mixture and the layer-by-layer method, a decrease in the R s value by eight and nine orders of magnitude, respectively, is observed compared with the reference fabrics. The electrical volume resistance (R v ) value is 1.30 × 10 12 Ω and 1.06 × 10 12 Ω (Figure 12b) for the mAr and pAr fabrics, respectively. After the 5-fold AgNW application, the R v value decreases by 10 orders of magnitude for both fabrics. After the AgNWs and silanes mixture and layer-by-layer modification, the R v values are lower than those of the unmodified fabrics by nine orders of magnitude.
The slightly higher values of R s and R v for the fabrics modified with silanes by the mixture and layer-by-layer method compared to the fabrics with only AgNWs are due to the presence of silanes, which, on aramid fabrics, have higher R s and R v values of 5.98 × 10 7 Ω and 3.77 × 10 7 Ω, respectively, for the mAr fabric and 3.30 × 10 8 Ω and 6.91 × 10 7 Ω, respectively, for the pAr fabric. Silanes can be a barrier to the flow of electrons through AgNWs. Moreover, higher values of both resistances are found for the mixture method than for the layer-by-layer method, which may be due to the AgNWs being covered by silanes, which limits their direct connection with each other (which can be seen in the SEM images, Figures 7c and 8c). On the other hand, for the layer-by-layer method, fibers that protrude above the silanes layer are densely covered with AgNWs, which create conductive paths. Under the silanes layer, both on the surface and between the fibers, there are AgNWs that connect with each other, which ensures a lower R v value compared to the fabrics modified with the mixture method.
Moreover, the lower values of R v in relation to R s for all modified fabrics may be due to the AgNWs filling the spaces between the fibers.
After UV irradiation, the R s values increase by one order of magnitude for both the AgNWs modified fabrics (Figure 12a). This increase may be caused by the degradation of AgNWs, which is visible in the SEM images as silver precipitates on the surface of the nanowires (Figures 7b and 8b). For the mixture method, the R s values increase by six orders of magnitude and the fabric becomes non-conductive. For the layer-by-layer method, the R s value has the same order of magnitude. These differences are related to the different thicknesses of the silanes layer. For the layer-by-layer method, the layer is thicker and protects the AgNWs from the UV radiation. In the case of the mixture method, the silanes coating that covers the AgNWs is thin and does not reflect the UV radiation as efficiently. For fabrics modified with the AgNWs and silanes mixture, the coating is discontinuous and damaged with numerous cavities and cracks (Figures 7c and 8c). This causes interruption percolating paths formed by the AgNWs, which prevent the flow of electrons.
The UV radiation causes an increase in the R v values for the AgNWs modified fabrics by one order of magnitude (Figure 12b). For the layer-by-layer method, the value only slightly increases. The R v values of mAr/RF/PD/5Ag+S increase but have the same order of magnitude. For pAr/RF/PD/5Ag+S, an increase by one order of magnitude is observed. The lower increase in R v compared to R s after irradiation is due to the fact that AgNWs located between the fibers inside the fabric are less exposed to UV radiation than the AgNWs on its surface.

Conclusions
Multifunctional metaand para-aramid fabrics modified with AgNWs and a mixture of silanes, APTES, and DEDMS, were obtained. The aim of the studies was to protect against UV radiation and improve the mechanical, electrical, and hydrophobic properties of modified aramid fabrics. New functionalization methods, a one-step method (mixture) with AgNWs dispersed in the silanes mixture, and a two-step method (layer-by-layer) in which the silanes mixture was applied on the previously deposited AgNWs layer, were developed.
Fabrics were pre-treated in a low-pressure air RF plasma, and a subsequent polydopamine coating was applied.
The modified fabrics acquired hydrophobic properties. The water contact angle for the metaand para-aramid fabric was 125 • and 120 • , respectively, for the mixture and 112 • and 114 • , respectively, for the layer-by-layer method. The surface free energy for the AgNWs and silanes modified fabrics is lower by about 30% for the meta-aramid fabric and 50% for the para-aramid fabric compared with the reference fabrics.
Better resistance to UV radiation was achieved for the layer-by-layer method. The UV radiation caused no changes in the layer-by-layer coating, while for the mixture coating, there was damage, and some coating fragments were detached. The UV radiation caused a significant decrease in the specific strength of the reference fabrics by about 50% and 60% for the metaand para-aramid fabric, respectively, while for the mixture and layer-bylayer method, the specific strength values were 71% and 63% higher for the meta-aramid fabric, respectively, and 102% and 110% higher for the para-aramid fabric, respectively. The layer-by-layer modified fabrics were the most abrasion resistant; before and after UV radiation, no thread damage was observed after 100,000 abrasion cycles. The electrical surface resistance for the layer-by-layer method was nine orders of magnitude lower than the reference fabrics, and for the mixture method, it was eight orders of magnitude lower. After UV irradiation, the R s did not change for the layer-by-layer method and increased by six orders of magnitude for the mixture modified fabrics, which became non-conductive. We selected the layer-by-layer method as the most effective for aramid fabric modification; it results in great surface, electrical, and mechanical properties and better resistance to UV radiation. It protects aramid fabrics from degradation and the deterioration of their functional properties.