Fabrication of Structural-Coloured Carbon Fabrics by Thermal Assisted Gravity Sedimentation Method

Structural-coloured poly(styrene-methyl methacrylate-acrylic acid) (Poly(St-MMA-AA)) deposited carbon fabrics (Poly(St-MMA-AA)/PCFs) with fascinating colours (salmon, chartreuse, springgreen, skyblue, mediumpurple) changing with the (Poly(St-MMA-AA) nanoparticle sizes can be facilely fabricated by the thermal-assisted gravity sedimentation method that facilitates the self-assembly of Poly(St-MMA-AA) colloidal nanoparticles to generate photonic crystals. The particle sizes of Poly(St-MMA-AA) copolymer with core/shell structure varying from 308.3 nm to 213.1 nm were controlled by adjusting the amount of emulsifier during emulsion polymerisation. The presence of the intrinsic chemical information of Poly(St-MMA-AA) copolymer has been ascertained by Raman and Fourier Transform Infrared (FT-IR) Spectroscopy analysis. Colour variation of the as-prepared structural-coloured carbon fabrics (Poly(St-MMA-AA)/PCFs) before and after dipping treatment were captured while using an optical microscope. The structural colours of Poly(St-MMA-AA)/PCFs were assessed by calculating the diffraction bandgap according to Bragg’s and Snell’s laws. The Poly(St-MMA-AA) photonic crystal films altered the electrical properties of carbon fabrics with the resistivity growing by five orders of magnitude. The differential electrical resistivity between Poly(St-MMA-AA)/PCFs and wet Poly(St-MMA-AA)/PCFs combined with the corresponding tunable colours can be potentially applied in several promising areas, such as smart displays, especially signal warning displays for traffic safety.


Introduction
Photonic crystal, an artificial crystal with highly periodic structures that are allowed to manipulate the propagation of light, has emerged as one of the promising optical materials for developing inherent structural colours, the studies of such materials possessing intrinsic structural colours by adjusting the photonic crystal bandgap into visible spectrum range has been conducted over the past few decades [1][2][3]. The bandgap derived from highly ordered periodic structures is responsible for uniformly reflected colours in the visible spectrum. Accordingly, a variety of techniques, like photolithography [4], screen printing [5], atomisation deposition [6], inkjet printing [7,8], spray coating [9,10], gravity sedimentation [11,12], and electrophoretic deposition [13,14], have been proposed for the adhibition by applying photonic crystals onto substrates in several applications, including paints and inks [5], smart windows [3], energy-saving devices [15], night-time traffic safety and advertisement display [16], anti-counterfeiting security [4,17,18], eyeglasses and photographic lenses [19], and information storage [20]. To realise such promising industrial applications, the studies on the large-area scalable fabrication technique of photonic crystals have been conducted, including melt-shear organization method [21] and oscillatory shear technique [22]. Zhao et al. [23] achieved large-scale assembly of

Preparation and Purification of Poly(St-MMA-AA) Nanoparticles
The experimental arrangement and method used for preparing Poly(St-MMA-AA) were similar to the previously reported emulsion polymerisation method [30]. Styrene (St) (20 g), methyl methacrylate (MMA) (1 g), acrylic acid (AA) (1 g), deionised water (100 g), sodium dodecyl sulfate (SDS) as an emulsifier (0.001-0.006 g), and then ammonium bicarbonate as a buffer (0.5 g) were sequentially added into a three-necked flask that was equipped with Nitrogen (N 2 ) atmosphere, a reflux condenser, and a magnetic stirrer at a stirring speed of 500 rpm. The reaction mixture was kept at a constant temperature (70 • C) controlled by Lab Companion RW3-0525 Refrigerated & Heating Bath Circulator (Hong Kong Labware Co., Ltd., Hong Kong SAR, China) for 30 min, and then heated to 80 • C, followed by the addition of an aqueous APS solution prepared by dissolving 0.48 g APS in 15 g deionised water. Polymerisation was carried out for 10 h with continuous stirring. The resulting colloidal P(St-MMA-AA) nanoparticles were purified several times by centrifugation at 14,000 rpm for 75 min at 22 • C and then re-dispersed in deionised water by ultrasonication. The schematic chemical structure of as-synthesised Poly(St-MMA-AA) is depicted as Scheme 1.
Nanomaterials 2020, 10, x FOR PEER REVIEW 3 of 16 methacrylate (MMA) (1 g), acrylic acid (AA) (1 g), deionised water (100 g), sodium dodecyl sulfate (SDS) as an emulsifier (0.001-0.006 g), and then ammonium bicarbonate as a buffer (0.5 g) were sequentially added into a three-necked flask that was equipped with Nitrogen (N2) atmosphere, a reflux condenser, and a magnetic stirrer at a stirring speed of 500 rpm. The reaction mixture was kept at a constant temperature (70 °C) controlled by Lab Companion RW3-0525 Refrigerated & Heating Bath Circulator (Hong Kong Labware Co., Ltd., Hong Kong SAR, China) for 30 min., and then heated to 80 °C, followed by the addition of an aqueous APS solution prepared by dissolving 0. 48

Generation of Poly(St-MMA-AA) Photonic Crystal Films on Carbon Fabrics
The stock solution of 8 wt.% Poly(St-MMA-AA) nanoparticles in suspension was used for preparing Poly(St-MMA-AA) photonic crystal films on carbon fabrics via the thermal assisted gravity sedimentation method, as shown in Scheme 2. A circular piece of fabric with a diameter of 2 cm was pre-added into a 20 mL glass bottle, followed by the addition of 2 mL nanoparticle suspension solution. Subsequently, the bottle was placed in a constant hot environment at 65 °C in a dry oven (Esco Isotherm® Forced Convection Laboratory oven that was purchased from Hong Kong Labware Co. Ltd, Hong Kong SAR, China) for heating treatment. After 12 h of gravity sedimentation and selfassembly, the solvents were evaporated, the particles got assembled in a closer arrangement, and the Poly(St-MMA-AA) photonic crystal films were finally formed on carbon fabrics, hereafter referred to as Poly(St-MMA-AA)/PCFs. Wet Poly(St-MMA-AA)/PCFs was acquired by dipping treatment into a beaker with 500 mL H2O for two seconds. Besides, carbon fabrics were pre-treated by a plasma system (Surfx technologies, Redondo Beach, CA, USA) before thermal-assisted gravity sedimentation. The samples were laid on a flat plate and the operating temperature in the plasma reactor was 60 °C with the treatment condition of 0.4 mm/s operating speed, 290 W power, and input oxygen and helium flow rate were 0.4 L/min. and 20 L/min., respectively.

Generation of Poly(St-MMA-AA) Photonic Crystal Films on Carbon Fabrics
The stock solution of 8 wt.% Poly(St-MMA-AA) nanoparticles in suspension was used for preparing Poly(St-MMA-AA) photonic crystal films on carbon fabrics via the thermal assisted gravity sedimentation method, as shown in Scheme 2. A circular piece of fabric with a diameter of 2 cm was pre-added into a 20 mL glass bottle, followed by the addition of 2 mL nanoparticle suspension solution. Subsequently, the bottle was placed in a constant hot environment at 65 • C in a dry oven (Esco Isotherm ® Forced Convection Laboratory oven that was purchased from Hong Kong Labware Co., Ltd., Hong Kong SAR, China) for heating treatment. After 12 h of gravity sedimentation and self-assembly, the solvents were evaporated, the particles got assembled in a closer arrangement, and the Poly(St-MMA-AA) photonic crystal films were finally formed on carbon fabrics, hereafter referred to as Poly(St-MMA-AA)/PCFs. Wet Poly(St-MMA-AA)/PCFs was acquired by dipping treatment into a beaker with 500 mL H 2 O for two seconds. Besides, carbon fabrics were pre-treated by a plasma system (Surfx technologies, Redondo Beach, CA, USA) before thermal-assisted gravity sedimentation. The samples were laid on a flat plate and the operating temperature in the plasma reactor was 60 • C with the treatment condition of 0.4 mm/s operating speed, 290 W power, and input oxygen and helium flow rate were 0.4 L/min and 20 L/min, respectively.
as Poly(St-MMA-AA)/PCFs. Wet Poly(St-MMA-AA)/PCFs was acquired by dipping treatment into a beaker with 500 mL H2O for two seconds. Besides, carbon fabrics were pre-treated by a plasma system (Surfx technologies, Redondo Beach, CA, USA) before thermal-assisted gravity sedimentation. The samples were laid on a flat plate and the operating temperature in the plasma reactor was 60 °C with the treatment condition of 0.4 mm/s operating speed, 290 W power, and input oxygen and helium flow rate were 0.4 L/min. and 20 L/min., respectively.

Water-in-Air Contact Angle (WCA) Measurement
Surface wettability properties of pristine and plasma treated carbon fabric were measured by SDS-350 Optical contact angle measuring instrument manufactured by Guangdong Dint Intelligent Technology Co., Ltd., Guangdong, China. The WCA measurement was performed by the method of applying a sessile of water that was placed on the surface of the specimens at room temperature.
The WCA values were tested immediately after each droplet of 2 µL water touched the surface of the target samples. The WCA values of the plasma treated carbon fabrics were recorded by time (0, 5,10,15,20,22,22,24, and 26 min).

Microscopic Observation
Transmission electron microscopy (TEM) morphologies of Poly(St-MMA-AA) nanoparticles were detected by JEOL JEM-2011 Transmission Electron Microscope. Prior to conducting TEM measurement, Poly(St-MMA-AA) nanoparticles were first pre-dispersed and diluted in aqueous solution to approximately 100 ppm, 10 µL nanoparticle solution were then deposited on 400-mesh carbon-coated copper (Cu) grids, and the sample was completely air-dried prior to TEM observation.

Particle Size and Polydispersity Indices (Ð) Measurement
The average colloidal Poly(St-MMA-AA) particle sizes and polydispersity indices of the as-synthesised silica nanoparticles in suspension were measured and calculated by a particle size analyser provided from Zeta Plus, Brookhaven Instruments Corp., Holtsville, NY, USA. Solid-state particle sizes of Poly(St-MMA-AA), Poly(MMA-AA) Shell, Polystyrene (PS) core were measured from TEM images while using Nano measurer software, version 1.2, Fudan University, Shanghai, China.

Optical Image Acquisition
Optical microscopic images of Poly(St-MMA-AA)/PCFs were examined using Leica M165 FC optical microscopy (Leica Microsystems, Newcastle, UK) integrated with 16.5:1 zoom optics. The images were captured at room temperature.
The photographs of Poly(St-MMA-AA)/PCFs were taken with a 12-megapixel rear camera with a 28 mm wide-angle lens and f/1.8 aperture. The images were acquired in a light chamber under D65 illumination source. No adjustment of colour, pixels, and contrast was applied to these pictures.

Fourier Transform Infrared (FT-IR) Spectroscopy
FT-IR spectrum with wave numbers from 400 cm −1 to 4000 cm −1 was obtained by subtracting the substrate effect using Thermo Scientific NicoletTM 380 FT-IR Spectrometer (Thermo Fisher Scientific,

Raman Spectroscopy
Micro-Raman spectrum ranged from 3200 to 300 cm −1 and it was measured by the Renishaw InVia Micro-Raman Spectroscopy system (Renishaw plc, Gloucestershire, UK) equipped with a confocal optical microscope for fast mapping. The Raman wavelength range was between 200 and 2200 nm, the spectral data was collected with resolution of 0.3 cm −1 , and the stability was <±0.001 cm −1 . The tested samples were irradiated with diode laser with excitation wavelength of 532 nm. The output power of laser was 5 mW, The Raman scatterings from the samples were collected by an objective lens, filtered into the microscope frame, and directed to a 50× eyepiece for visual observations. A multichannel charge-coupled device (CCD) detector was used for spectral analyses, and a digital camera with high sensitivity mode was applied for imaging.

Colour Property Measurement
Colour reflectance of Poly(St-MMA-AA)/PCFs was performed by an SF650 DataColour spectrophotometer from DataColor International (Lawrenceville, NJ, USA) with the D65 illumination source, and the aperture size was 9 mm. Reflectance in the wavelength in the range from 400 to 700 nm were obtained. Each datum was acquired by calculating the average value of four repeated measurements. The CIE L*a*b* values of the Poly(St-MMA-AA)/PCFs samples before and after dipping were tested by Datacolour ColourReader Pro portable spectrophotometer with 8 high CRI, white LED's light source, and OLED (Organic Light Emitting Diodes) display.

Electrical Resistivity Measurement
The surface resistivity of the specimens (carbon fabrics and wet Poly(St-MMA-AA)/PCFs) with smaller resistivity was measured by a four-probe method at room temperature with ST-2258A multifunction digital four-probe tester that was equipped with ST2558B-F01 Linear square resistance four probe (Suzhou Jingge Electronic Co., Ltd., Jiangsu, China), whereas the resistance of Poly(St-MMA-AA)/PCFs samples with higher resistivity was tested by FLUKE 15b+ digital multimetre (Fluke Corp., Washington, DC, USA) with the assistance of two copper electrodes at both ends of the tested sample. The final surface resistivity or resistance was obtained by performing five replications at different locations on the sample and the average value was calculated for analysis. The thickness of the samples was tested by SanLiang digital indicators, Sanliang Measuring Tool Co., Ltd., Dongguan, China.

WCA Analysis of Carbon Fabrics
Water contact angles (WCA) of both pristine and plasma-treated carbon fabrics were collected, as depicted in Figure 1a, and the result shows that the plasma-treated carbon fabrics with a mean contact angle of 126.4 • had improved surface wettability, approximately 16 • of angle lower than the pristine carbon fabric with contact angle reaching 142.1 • on average, which demonstrates that the initial infiltration of plasma-treated carbon fabrics into colloidal suspension would be faster than pristine carbon fabrics, and plasma treatment with the function of increasing wettability contributes to making carbon fabrics become more promising candidates as the substrates for the formation of photonic crystals on them through thermal assisted gravity sedimentation. From Figure 1b, a set of contact angles of the plasma treated carbon fabric decreasing by time has been recorded, which shows that during the first 15 min, contact angles of carbon fabric had no obvious changes. As more time lapsed, the contact angle reached 0 • after 26 min of absorption, which indicated that the carbon fabric was totally infiltrated. The complete infiltration time (26 min) of plasma-treated carbon fabrics is extremely shorter than the time of sedimentation process (12 h), which might cause a slight effect on the interactions between colloidal nanoparticles in suspension and the plasma-treated substrates. It has been proved from the result of contact angle test that the carbon fabrics would become more hydrophilic than the untreated one, and plasma treatment tends to be favourable for the formation of stronger binding force between the plasma-treated carbon fabrics and the colloidal nanoparticles with surrounding hydrophilic group (-COOH) on the surface of shell part, as presented in Figure 2b.

TEM Observation and Particle Size Analysis
The schematic structure of Poly(St-MMA-AA) nanoparticle is simulated, as depicted in Figure  2a, and it has been proved by TEM observations (Figure 2b [42]. In this work, SDS as the variate with weight ratios of 0.001 g to 0.006 g has been added to generate diverse particle sizes. In the present investigation, variations Raman spectroscopy was utilised in order to elucidate the nanostructures of pristine and plasma-treated carbon fabrics (Figure 2c) it can be found that there is no obvious change in the surface structure of carbon fabric before and after plasma treatment; however, the spectrum shows two major changes in the peak shifts of 1604 cm −1 (G peak) and 1314 cm −1 (D peak). The peak located at 1604 cm −1 represents the typical graphite crystallite structure, which belongs to the in-plane bond stretching of carbon atom, while the peak with higher intensity at 1314 cm −1 refers to the disordered carbon structure, corresponding to the vibration of crystallite component.
Poly(St-MMA-AA) colloidal nanoparticles with hydrodynamic interactions in the aqueous dispersion and they impeded the accurate measurement of particle size when tested using Zeta particle size analyser, and the particles were in swollen form in aqueous medium, which resulted in the larger particle size result. The particle samples were pre-treated by drying in order to achieve the removal of media, which results in the shrinkage of nanoparticles as compared to that from Zeta analyser and it is proposed to obtain the decrease of particle size after water evaporation. 002 g, 0.003 g, 0.004 g, and 0.006 g, respectively (from Zeta particle sizer); (f) particle size contrast of Poly(St-MMA-AA) nanoparticles measured by Zeta analyser and by Nano measurer 1.2 software from TEM micrographs.

TEM Observation and Particle Size Analysis
The schematic structure of Poly(St-MMA-AA) nanoparticle is simulated, as depicted in Figure 2a, and it has been proved by TEM observations (Figure 2b array [42]. In this work, SDS as the variate with weight ratios of 0.001 g to 0.006 g has been added to generate diverse particle sizes. In the present investigation, variations of particle size by the change of SDS amount were analysed in Figure 2e. The polymerisation does not start in the emulsifier (SDS) micelles, but in the aqueous phase after initiating of the initiator (APS), followed by the formation of radicals, according to the micellar mechanism of the particle formation by emulsion polymerisation as elucidated before (comprise particle nucleation and growth stage). Primary charged polymer particles are generated by precipitation of oligomer radicals, while they are saturated after reaching the critical micelle concentration (CMC) according to Fitch and Tsai's findings [43,44], which combines with other soluble radicals again to form the neutral surface active substances, and finally flocculating appears as the reaction of the other radicals with the solubility is terminated [45]. SDS emulsifier contributes to dispersing and stabilising of the particles and it also leads to an increase in the solubility of the radicals during the above formation [46]. There was a hydrogen bond that formed between SO 4 − Na + of SDS and -COOH group (see Figure 2b) surrounded on the particle peripheries, which is conducive to encapsulating around the particle in order to provide a stable emulsion environment.
Hansen et al. [47] showed the decreasing number of new particles was due to the decrease of free emulsifier (SDS) concentration beneath CMC, which implies that the increasing concentration of SDS would increase the new particle number contributing to form larger particle aggregates. Accordingly, the growth trend of Poly(St-MMA-AA) nanoparticle size was induced on the whole with the increasing weight ratios of SDS from 0.001 g to 0.006 g that caused a highly number of primary particles and consequently resulted in smaller particle size, along with the Poly(St-MMA-AA) hydrodynamic particle size decreasing from 308.3 nm to 213.1 nm. Figure 2f allows for a comparison of particle sizes (diameter) of Poly(St-MMA-AA) by both the particle size analyser and TEM micro-images. It is notable that the average particle sizes of three-size nanoparticles that were measured from TEM micro-images were approximately 30 nm smaller than that obtained using Zeta analyser. The different results of particle sizes are attributable to the discrepancy of the nanoparticle measuring environment; in other words, Brownian dynamics of Poly(St-MMA-AA) colloidal nanoparticles with hydrodynamic interactions in the aqueous dispersion and they impeded the accurate measurement of particle size when tested using Zeta particle size analyser, and the particles were in swollen form in aqueous medium, which resulted in the larger particle size result. The particle samples were pre-treated by drying in order to achieve the removal of media, which results in the shrinkage of nanoparticles as compared to that from Zeta analyser and it is proposed to obtain the decrease of particle size after water evaporation.  [48,49]. The characteristic peaks that are observed in the fingerprint region at 1031 cm −1 and 910 cm −1 wavenumbers are attributed to C-O-C symmetric stretching vibration, which is associated with the C-COOCH 3 group of MMA located at the shell region of nanoparticles [50], the intensities of these peaks are weak because of the small amount of MMA monomer involved in the synthetic process, while the peak at 1604 cm −1 can be associated with -C=C stretching vibrations of aromatic double bond in styrene molecule. The several peaks at 1943 cm −1 , 1870 cm −1 , and 1807 cm −1 in the region of 1800-2000 cm −1 are expected for weak overtone and combination bands of mono-substituted aromatic rings [51][52][53]. The signal corresponding to the deformation of C-H bonds in the methyl group is confirmed at 1456 cm −1 . These vibrational peaks indicate the existence of benzene rings in the core segment of as-synthesised nanoparticles. The pronounced peaks at 2929 cm −1 and 2856 cm −1 are obtained due to the asymmetric and symmetric stretching vibration of aliphatic C-H bond of CH 2 , and flexion of C-H in the plane contribute to the presence of 1064 cm −1 wavenumber [54]. The peaks generating at 767 cm −1 and 707 cm −1 are significantly associated with the flexural vibrations of C-H group. The results of FT-IR analysis demonstrate the existence of each chemical functional group of copolymer Poly(St-MMA-AA), and the spectra provides confirmatory evidence that monomer styrene (St), methyl methacrylate (MMA), and acrylic acid (AA) have incorporated with each other to produce Poly(St-MMA-AA) through emulsion polymerisation reaction, which is also consistent with experimental observation from Lai's group reported in the literature [55].

Chemical Characteristics by FT-IR and Raman Spectroscopy
aromatic double bond in styrene molecule. The several peaks at 1943 cm −1 , 1870 cm −1 , and 1807 cm −1 in the region of 1800-2000 cm −1 are expected for weak overtone and combination bands of monosubstituted aromatic rings [51][52][53]. The signal corresponding to the deformation of C-H bonds in the methyl group is confirmed at 1456 cm −1 . These vibrational peaks indicate the existence of benzene rings in the core segment of as-synthesised nanoparticles. The pronounced peaks at 2929 cm −1 and 2856 cm −1 are obtained due to the asymmetric and symmetric stretching vibration of aliphatic C-H bond of CH2, and flexion of C-H in the plane contribute to the presence of 1064 cm −1 wavenumber [54]. The peaks generating at 767 cm −1 and 707 cm −1 are significantly associated with the flexural vibrations of C-H group. The results of FT-IR analysis demonstrate the existence of each chemical functional group of copolymer Poly(St-MMA-AA), and the spectra provides confirmatory evidence that monomer styrene (St), methyl methacrylate (MMA), and acrylic acid (AA) have incorporated with each other to produce Poly(St-MMA-AA) through emulsion polymerisation reaction, which is also consistent with experimental observation from Lai's group reported in the literature [55].    Figure 4. Based on the assignment of Raman active lines, the characteristic peak that was detected at 3055 cm −1 was due to aromatic C-H stretching vibration referring to the core information of the copolymer [56]. The peak at 2906 cm −1 indicating the stretching of -CH 2 or C-H group can be found. The peaks at 842 and 1199 cm −1 represent C-COOH stretching and C-O stretching coupled with in-plane bending related to shell composition, respectively [57]. Raman scattering from the aromatic ring skeletal stretch and ring deformation mode about the core part of the copolymer Poly(St-MMA-AA) is also detectable at 1603 and 620 cm −1 [58]. Poly(St-MMA-AA)/PCFs shows a stronger peak at 1603 cm −1 when compared with Poly(St-MMA-AA) nanoparticles, mainly due to the effect of crystallite structure of carbon fabric substrate. It is notable that the typical one at 1001 cm −1 showing a strong marker is the most prominent, which is due to the breathing mode of aromatic ring that had an intense aromatic carbon-carbon bond stretch [58,59]. It is related to the polystyrene core of the Poly(St-MMA-AA) nanoparticle. The characteristic band at 794 cm −1 is the vibrational mode of phenyl rings group that are present in the core segment of the copolymer [59]. 1030 cm −1 corresponds to C-H in-plane deformation, 1156 cm −1 is C-C stretch, and the peak appearing at 1449 cm −1 indicates CH 2 scissoring of core (PS) composition [58,60]. The Raman spectra also show the characteristic band at 3002 cm −1 and this band indicates the vibration of C-H of O-CH 3 , while the peak at 1328 cm −1 confirms the vibration of C-COO group, which indicates the presence of Poly(MMA-AA) shell composition [61]. The presence of the intrinsic chemical information of Poly(St-MMA-AA) copolymer could be ascertained with the observation from the combination of Raman and FT-IR analysis.
1449 cm −1 indicates CH2 scissoring of core (PS) composition [58,60]. The Raman spectra also show the characteristic band at 3002 cm −1 and this band indicates the vibration of C-H of O-CH3, while the peak at 1328 cm −1 confirms the vibration of C-COO group, which indicates the presence of Poly(MMA-AA) shell composition [61]. The presence of the intrinsic chemical information of Poly(St-MMA-AA) copolymer could be ascertained with the observation from the combination of Raman and FT-IR analysis.     In optical micrographs, the colours had a red hue when the particle size decreased to 249.7 nm and then turned to a green hue with a further decrease of particle diameter. The inserts in Figure 5c-g shows the photograph of Poly(St-MMA-AA)/PCFs with the structural colours (salmon, chartreuse, springgreen, skyblue, mediumpurple) (left to right) as the Poly(St-MMA-AA) particle diameters changed from 308.3 nm to 213.1 nm. This is in good agreement with experimental results of reflectance, as displayed in Figure 6. The resulting reflected wavelength with the maximum amplitude of specific wavelength (λmax) at 650, 570, 520, 490, and 440 nm can be predicted by the Bragg's and Snell's laws [64,65], commensurate to different Poly(St-MMA-AA)/PCFs differing from particle size of 308.3, 262.4, 249.7, 234.1, and 213.1 nm, which produce brilliant colours from salmon, chartreuse, spring green, skyblue to medium purple, a blue-hue occurs in the spectra would occur. The theoretical diffraction peak position of the spectra (λi) could be empirically calculated as Equation (1) [55,66], as the lattice was in close-packed structure (face-centred cubic, fcc),

Colour Measurement
where, D Pi is the diameter of Poly(St-MMA-AA) nanoparticle, f P is the filling ratio of the nanoparticles (the value is 0.74 in fcc [26]), θ means the normal incident angle (θ = 0 • , the direction of incident light was perpendicular to the ordered photonic crystal film), and n e f f is the effective refractive index of the photonic crystal film structure that could be obtained from Equation (2) [65], where, n P is the refractive index of Poly(St-MMA-AA) nanoparticle (n P = 1.5916) and n m is the refractive index of air (n air = 1).
Nanomaterials 2020, 10, x FOR PEER REVIEW 11 of 16 .      (Table 1), where L*, a*, b* correspond to the degree of lightness, red/green coordinates, yellow/blue coordinates to investigate the effect of variations of Poly(St-MMA-AA) diameters on the ultimate structural colour. CIE colourimetry could intuitively reflect the colour variation and decode the colours with quiet For instance, particle size of Poly(St-MMA-AA)/PCF with salmon colour, the particle size measured in suspension (by Zeta) was 308.3 nm, while the particle size in dry state for TEM observation was 268.5 nm (as shown in Figure 2d), which is taken for Bragg calculation according to the formula of Equation (1) and Equation (2); hence, λi can be obtained with the value of 640.6 nm. The experimental data with photonic bandgap position (λmax = 650 nm), as mentioned above, do not deviate appreciably from this theoretical result of λi. The ultimate surface cracks, defects, and loose-packed structures of the Poly(St-MMA-AA) photonic crystal film on carbon fabrics, as presented in Figure 5c-g, should be responsible for the subtle difference (less than 10 nm) between the experimental and theoretical results. The enlarged lattice interlayer spacing of the crystalline planes would cause the increase of diffraction peak wavelength if it was not densely-packed structure, resulting in a numeric value λmax of the experimental value greater than the theoretical one λi. Therefore, a red shift from the theoretical value to experimental value could appear, which matches the findings reported in extant literature [55,65]. As the peak wavelengths refer to the colours of Poly(St-MMA-AA)/PCFs in visible spectrum at the top of reflectance curve profile in Figure 6, the simulative colours could be estimated by assessing from the diameters of as-synthesised Poly(St-MMA-AA) nanoparticles, since the colour change by calculation is in accordance with the perceptual colour difference that is shown in the insert of Figure 5c-g. Figure 5h-l show photos of the corresponding samples after dipping treatment. The colours of the insert images were enhanced. Since water medium was filled in the lattice spacing, n m in this situation should be the refractive index of water larger than that of air, which swells the periodic interplanar spacing, and the bandgap position is increased. Consequently, a red shift of colours is caused by dipping treatment and the colour difference that existed between Poly(St-MMA-AA)/PCFs in the dry state and wet state.
The colour difference between Poly(St-MMA-AA)/PCFs with the adjacent nanoparticle sizes can be analysed by Commission Internationale de l'Eclairage (CIE) L*a*b* coordinates (Table 1), where L*, a*, b* correspond to the degree of lightness, red/green coordinates, yellow/blue coordinates to investigate the effect of variations of Poly(St-MMA-AA) diameters on the ultimate structural colour. CIE colourimetry could intuitively reflect the colour variation and decode the colours with quiet precise data. Parameter ∆a* represents the discrepancy in red and green, from 308.3 nm to 249.7 nm, the value of ∆a* is negative (−12.73, −10.78), which indicates that the structural colour became greener along with the decrease of nanoparticle sizes. Conversely, the colour turned to be redder (positive values of ∆a*: 9.86, 7.49) with the further decrease of particle diameters. Similarly, for ∆b*, the positive and negative values refer to yellower and bluer change in structural colour, respectively. Consequently, as the particle sizes decreased from 308.3 nm to 213.1 nm, the colour first turned from yellowish to blueish and eventually became yellow shift. The total colour difference ∆E ab * between every two adjacent colours has been given as Equation (3)

Electrical Resistivity of Poly(St-MMA-AA)/PCFs
The electrical resistivity of pristine, plasma-treated carbon fabric, Poly(St-MMA-AA)/PCFs, and wet Poly(St-MMA-AA)/PCFs obtained by dipping treatment with different particle sizes has been measured, as shown in Figure 7. After plasma treatment, surface wettability of carbon fabrics is significantly improved, but the coarse surface that is induced by plasma slightly reduces the conductivity of carbon fabrics and simultaneously increase the resistivity from 0.953 to 1.170 Ω·cm. The experimental results also showed that the resistivity was obviously increased after deposition of Poly(St-MMA-AA) photonic crystal film on the carbon fabrics as compared to pure carbon fabrics, because the deposition of Poly(St-MMA-AA) nanoparticles on the surface of carbon fabrics and the regions inside the cracks, defects, and spacing among the carbon fibre filaments impeded the conductive path, which resulted in the increase of resistivity by five order of magnitudes. As the size of Poly(St-MMA-AA) nanoparticle decreases from 308.3 nm to 213.1 nm, resistivities of Poly(St-MMA-AA)/PCFs before dipping treatment ranged from 3.25 × 10 5 to 5.16 × 10 5 Ω·cm. However, the corresponding resistivities after dipping treatment ranged from 9.36 × 10 2 to 9.66 × 10 2 Ω·cm. When considering the dipping treatment that is regarded as rainy days in our real life, the intrinsic decrease of resistivity on the wetting surface is attributed to water trapped at the free space between nanoparticles. The water indeed contributes to propagation of conductive path along the particle film. As particle diameter becomes smaller, the packing density becomes lower and vice versa, as illustrated from the graphical plots of resistivity vs. particle diameter in Figure 7. The resistivity difference for larger particle diameter such as 308.3 nm is smaller when compared to that with smaller particle diameter. In other words, smaller sized particles with lower particle packing density facilitate more free space or gap filled with water between adjacent particles, resulting in a large variation in resistivity difference between the dry and wet state.

Conclusions
In conclusion, this study has successfully shown that preparation of Poly(St-MMA-AA)/PCFs with desirable vivid structural colours transforming remarkably from salmon to medium purple for the control of the Poly(St-MMA-AA) sizes by adjusting the quantity of the emulsifier is feasible. The concentric shape of Poly(St-MMA-AA) with Poly(MMA-AA) shell and PS core, as well as the

Conclusions
In conclusion, this study has successfully shown that preparation of Poly(St-MMA-AA)/PCFs with desirable vivid structural colours transforming remarkably from salmon to medium purple for the control of the Poly(St-MMA-AA) sizes by adjusting the quantity of the emulsifier is feasible.