Measurement of the Heat Transfer Properties of Carbon Fabrics via Infrared Thermal Mapping

: The aim of this paper is to determine the heat transfer properties of biaxial carbon fabrics of different architectures, including non-crimp stitch bonded fabrics, plain, twill and satin woven fabrics. The speciﬁc heat capacity was determined via DSC (differential scanning calorimetry). A novel method of numerical analysis of temperature maps from a video using a high-resolution thermal camera is investigated for the measurement of the in-plane and transverse thermal diffusivity and conductivity. The determined thermal conductivity parallel to the ﬁbers of a non-crimp stitch bonded fabric agrees well with the theoretical value calculated employing the rule of mixtures. The presence of voids due to the yarn crossover regions in woven fabrics leads to a reduced value of transverse thermal conductivity, especially in the single ply measurements of this study.


Introduction
Heat transfer plays an important role in all stages of composite manufacturing. Heating in preforming is used to melt the thermoplastic matrix or binder so the fabric can be deformed and the layers consolidated [1,2] and also cure the adhesive binder for thermosetting binders [3,4]. Preforming takes place in single (SDF) [5] or double diaphragm forming (DDF) [6,7] or matched tool forming [8]. Mainstream composite manufacturing techniques [9] include autoclave processing [9], resin transfer molding (RTM) [10,11], vacuum-assisted resin infusion (VARI) [12], automated fiber placement (AFP) [13][14][15], thermoforming [16,17] and pultrusion [18,19]. Controlled heating is used in all techniques in combination with pressure or vacuum to reduce the matrix viscosity to facilitate resin flow, impregnation or bleeding and layer consolidation as well as to effect solidification via curing for reacting resins, especially thermosets, or cooling for thermoplastic matrices. Product design and process optimization in composite manufacturing is usually conducted via computer simulations in which the heat transfer equation is of particular significance.
The thermal properties of the composite material and the contact resistance at interfaces [20] are key properties in the heat transfer equation that need to be measured and inputted in the computer algorithms. The rule of mixtures or modifications could be used to predict the density and specific heat capacity of a composite material [21,22], both of which are isotropic properties. The specific heat capacity is also measured using differential scanning calorimetry (DSC) [21].
However, it is more difficult to determine the thermal conductivity which is a property depending on the fiber direction or the direction of nano-reinforcements for particulates with an aspect ratio, such as carbon nanotubes, nanofibers and graphene or graphene oxide which may be either randomly oriented in usual mixing, casting, coating via doctor blade or spraying techniques [23][24][25] or oriented via electrophoresis [26] or electrospinning [27], for example. For unidirectional reinforcements, the rule of mixtures may be used to predict the thermal conductivity in the direction parallel to the fibers [28]. As heat transfer is dominant through the laminate thickness, the thermal conductivity in the direction transverse to the fibers is critical. It can be predicted by the harmonic mean [28] also known as the inverse rule of mixtures, but that indicates the lower bound on the composite conductivity [29,30]. The next best constitutive relation for the thermal conductivity of a composite transverse to the fibers, k c,t , is given by Clayton's model [31,32]: where k m and k f,t are the thermal conductivity of the matrix (or air for dry reinforcements) and transverse thermal conductivity of fibers, respectively, and V f is the fiber volume fraction. It must be said that a range of values have been reported for the transverse and axial thermal conductivity of carbon fibers, depending on precursor, manufacturing route, treatment and temperature [33]. Modeling becomes even more complicated for multilayer or woven fabrics, pointing to the necessity of measuring the thermal conductivity. The main issue in the measurement of thermal conductivity is to account for the contact resistance [20]. Standardized Hukseflux THISYSTMTM and THASYSTMTM devices have been used for the measurements of the transverse and in-plane thermal conductivity, respectively [31]. They both include two samples sandwiched between a central thin heater and two outer heat sinks. A known heat flux is applied and temperature is measured at the heater and each heat sink: from these values and the dimensions of the samples, the thermal conductivity is determined according to Fourier's law. The contact resistance may be reduced by immersion in glycerol [31] but this would not be recommended for dry fabrics as the glycerol would infiltrate and loosen the fabric structure. In fact, as glycerol is still used for the rest of the contact surfaces, El-Hage et al. [33] sealed the dry fabric samples to avoid glycerol infiltration. They found that the through-thickness thermal conductivity of non-crimp carbon fabrics and twill woven carbon fabrics increased with increasing fiber fraction up to when a plateau was reached at about V f = 0.43 and 0.50, respectively, which might be attributed to the corresponding increase in contact points and contact area up to the packing fraction. Beyond these studies [31,33], there have been no further developments in the technique for measuring the thermal conductivity of textiles in composite materials.
The use of infrared (IR) thermal mapping may be a better method to focus on the heat transfer inside the sample area only to determine its thermal conductivity and then move to the interface to determine the interface contact resistance. This novel technique has been recently developed in our group [34] to measure the thermal conductivity of a thermoelectric wearable textile and the individual materials of its composite structure. Hence, this latest novel technique will be investigated in this study to determine both the through-thickness transverse and in-plane conductivity of fabrics in this work, in particular with regard to the diaphragm forming process, as illustrated in Figure 1. The aim of this study is to determine the heat transfer properties of 0/90 • biaxial fabrics of different architectures, including a non-crimp stitch bonded fabric, plain, twill and satin woven fabrics, and compare the values with the predictions of Clayton's model.  Figure 2 displays micrographs of the four fabrics tested in this study, where these images were obtained using a KEYENCE VHX-7000 digital microscope in transmission mode. A biaxial, non-crimp, 10 k carbon fiber fabric NCF300-biaxial (Figure 2a Figure 2 displays micrographs of the four fabrics tested in this study, where these images were obtained using a KEYENCE VHX-7000 digital microscope in transmission mode. A biaxial, non-crimp, 10 k carbon fiber fabric NCF300-biaxial (Figure 2a) of an areal density of 300 g m −2 and a measured uncompressed thickness of 0.70 mm. The NCF consisted of two identical plies at 0/90 • orientation, held together with a polyester yarn in a straight plain stitch pattern with a pitch of 5 mm. A plain woven carbon fabric A0186/000 (Fothergill Engineered Fabrics, UK) ( Figure 2b Figure 2 displays micrographs of the four fabrics tested in this study, where these images were obtained using a KEYENCE VHX-7000 digital microscope in transmission mode. A biaxial, non-crimp, 10 k carbon fiber fabric NCF300-biaxial (Figure 2a) of an areal density of 300 g m −2 and a measured uncompressed thickness of 0.70 mm. The NCF consisted of two identical plies at 0/90° orientation, held together with a polyester yarn in a straight plain stitch pattern with a pitch of 5 mm. A plain woven carbon fabric A0186/000 (Fothergill Engineered Fabrics, UK) ( Figure 2b Figure 2 displays micrographs of the four fabrics tested in this study, where these images were obtained using a KEYENCE VHX-7000 digital microscope in transmission mode. A biaxial, non-crimp, 10 k carbon fiber fabric NCF300-biaxial (Figure 2a) of an areal density of 300 g m −2 and a measured uncompressed thickness of 0.70 mm. The NCF consisted of two identical plies at 0/90° orientation, held together with a polyester yarn in a straight plain stitch pattern with a pitch of 5 mm. A plain woven carbon fabric A0186/000 (Fothergill Engineered Fabrics, UK) ( Figure 2b

Measurement of the Specific Heat Capacity
The specific heat capacity of all the fabrics and the silicone rubber diaphragm was determined via differential scanning calorimetry (DSC) experiments, using a TA Instruments DSC Q1000. A DSC scan was carried out in the temperature range of 15-140 • C, at a rate of 5 • C min −1 .

Measurement of the Thermal Conductivity
The thermal diffusivity was determined from the analysis of temperature map videos captured using a thermal imaging IR camera, FLIR A300 with a high magnification lens (25 µm resolution). Figure 3 displays the two set ups for the measurement of the transverse (though-thickness) and longitudinal (one of the in-plane directions) thermal diffusivity. For the measurement of the transverse diffusivity, the fabric was placed on the hot plate (Fisher Scientific 280 mm × 280 mm Digital Hotplate), covered by the silicone rubber diaphragm and secured in place using a weight on the top (Figure 3a,b). The camera faced the free thin side of the fabric as shown in Figure 3a. For the measurement of the longitudinal thermal diffusivity, the fabric was partly placed on the hot plate and was partly left "hanging" out of the plate as in a cantilever plate set up, with a thin support at the end so the fabric would remain flat during the experiment. The camera faced the free thin side of the fabric between the hot plate and the support.
Initially, the hot plate was at room temperature when the materials were assembled on top of it. To setup the camera and find the correct focus point, a piece of paper was used to not preheat any of the materials. The location was then marked so the fabric could be placed onto the hot plate in the correct position and was not preheated before the experiment began. During the experiment, the hot plate was heated from room temperature, T room = 20 • C, to 100 • C, mimicking the conditions in preforming where heating to 90-100 • C is required to activate the binder. The temperature images from the IR camera were video recorded at a frame rate of 30 Hz. All post-processing was carried out using the FLIR Tools+ software. The hot plate temperature was monitored using type-K thermocouples and recorded on a PICO thermocouple datalogger. For each type of fabric and conductivity measurement, 2-3 repeat experiments were carried out. The following heat transfer equation was applied for the fabric face opposite the camera: where T is temperature, T a is the ambient temperature, t is time, x i is the dominant direction of heat flow, the transverse direction x T for Figure 3a,b to measure the through-thickness transverse conductivity k T , and the longitudinal direction x ll for Figure 3c to measure the longitudinal conductivity k ll . ρ is the fabric density, calculated from the areal density of fabric, ρ a , divided by the fabric thickness as measured during the experiment with a micrometer and the IR camera photographs. While it is expected that the fabric is uncompressed in the measurement of the longitudinal conductivity, it is compressed in the measurement of the transverse conductivity. The fabric volume fraction is also calculated from its density, considering that it consists of carbon fiber (ignoring the stitch and binder mass) of a density of 1760 kg m −3 . c p is the specific heat capacity of the fabric measured from the DSC experiments. h is the heat transfer coefficient between the fabric and the air and l is the boundary layer length of this heat transfer due to natural convection. Equation (2) is discretized following the time implicit finite volume/finite difference technique [34][35][36] yielding: where superscripts n and n + 1 are the previous and current times, ∆t is the timestep between n + 1 and n times, and subscripts j − 1, j, j + 1 (or their midpoints j + 1/2, j − 1/2) denote successive discrete points in the x i axis or the variable T at those locations. In general, triads of points were selected in the transverse direction (through-thickness) within the fabric and the silicone rubber diaphragm, as depicted in Figure 4a, or in the longitudinal direction, as depicted in Figure 4b, in images of temperature maps to use Equation (3) at different times in the temperature map video obtained from the IR thermal camera. The temperatures at these points were obtained, so an X-Y plot was constructed according to Equation (3): assumed represented by the intercept of the linear fit. Using the cp value obtained from the DSC experiments, the transverse and longitudinal thermal conductivities were deter mined from the transverse and longitudinal thermal diffusivities, respectively. According to the discretization method in Equation (3), the method of determining the thermal dif fusivity (and hence thermal conductivity) is second-order accurate with regard to th space interval between two consequent points in each triad of points j − 1, j, j + 1 selected for the numerical analysis. Then, Equation (3) was linearly fitted to obtain the thermal diffusivity k i / ρc p from the gradient of the line, where a constant rate of heat loss to the ambient environment was assumed represented by the intercept of the linear fit. Using the c p value obtained from the DSC experiments, the transverse and longitudinal thermal conductivities were determined from the transverse and longitudinal thermal diffusivities, respectively. According to the discretization method in Equation (3), the method of determining the thermal diffusivity (and hence thermal conductivity) is second-order accurate with regard to the space interval between two consequent points in each triad of points j − 1, j, j + 1 selected for the numerical analysis.  (Figure 5a), which agrees with the literature [37] reporting c p = 1.3 J g −1 K −1 at room temperature for a silicon rubber of density 1100 kg m −3 . The unidirectional NCF exhibits the lowest c p , varying from 0.12 J g −1 K −1 at 30 • C to 0.25 J g −1 K −1 at 138 • C (Figure 5b). This agrees with the measured low c p value of 0.1 g −1 K −1 at room temperature for pure graphite [38]. As fabrics are formed in biaxial stitched or woven structures, more air is incorporated in the structure of higher c p = 1 J g −1 K −1 [39] than graphite, increasing the overall c p value of the fabric. NCF300biaxial has a c p varying from 0.67 J g −1 K −1 at 30 • C to 0.82 J g −1 K −1 at 138 • C (Figure 5c). According to the material specifications, the polyester stitch has a glass transition of 80 • C and melting point of 260-270 • C, and the binding agent has a melting point of 110 • C. No endothermic effects indicating glass transition of the stitch or melting of the binder are visible in the DSC curves, which may be due to the fact that the amount of binder (below 5 wt%) and stitch in the sample pan on the DSC instrument are negligible in their effect on heat flow. capacity, cp, as a function of temperature. The results clearly show an almost linear rela-tionship of the specific heat capacity as a function of temperature for most parts of each curve. The dip at the end of the cp graphs indicates the end of the test a little before 140 °C. The silicone rubber seems to have the highest cp value, varying from 1.3 J g −1 K −1 at 30 °C to 1.4 J g −1 K −1 at 138 °C (Figure 5a), which agrees with the literature [37] reporting cp = 1.3 J g −1 K −1 at room temperature for a silicon rubber of density 1100 kg m −3 . The unidirectional NCF exhibits the lowest cp, varying from 0.12 J g −1 K −1 at 30 °C to 0.25 J g −1 K −1 at 138 °C (Figure 5b). This agrees with the measured low cp value of 0.1 g −1 K −1 at room temperature for pure graphite [38]. As fabrics are formed in biaxial stitched or woven structures, more air is incorporated in the structure of higher cp = 1 J g −1 K −1 [39] than graphite, increasing the overall cp value of the fabric. NCF300-biaxial has a cp varying from 0.67 J g −1 K −1 at 30 °C to 0.82 J g −1 K −1 at 138 °C (Figure 5c). According to the material specifications, the polyester stitch has a glass transition of 80 °C and melting point of 260-270 °C, and the binding agent has a melting point of 110 °C. No endothermic effects indicating glass transition of the stitch or melting of the binder are visible in the DSC curves, which may be due to the fact that the amount of binder (below 5 wt%) and stitch in the sample pan on the DSC instrument are negligible in their effect on heat flow.  The plain weave has a cp varying from 0.78 J g −1 K −1 at 30 °C to 1 J g −1 K −1 at 138 °C ( Figure 6a). The 4 × 4 twill weave has a cp varying from 0.57 J g −1 K −1 at 30 °C to 0.7 J g −1 K −1 at 125 °C (Figure 6b). The 5H satin weave has a cp varying from 0.75 J g −1 K −1 at 30 °C to 0.94 J g −1 K −1 at 138 °C (Figure 6c). capacity, cp, as a function of temperature. The results clearly show an almost linear relationship of the specific heat capacity as a function of temperature for most parts of each curve. The dip at the end of the cp graphs indicates the end of the test a little before 140 °C. The silicone rubber seems to have the highest cp value, varying from 1.3 J g −1 K −1 at 30 °C to 1.4 J g −1 K −1 at 138 °C (Figure 5a), which agrees with the literature [37] reporting cp = 1.3 J g −1 K −1 at room temperature for a silicon rubber of density 1100 kg m −3 . The unidirectional NCF exhibits the lowest cp, varying from 0.12 J g −1 K −1 at 30 °C to 0.25 J g −1 K −1 at 138 °C (Figure 5b). This agrees with the measured low cp value of 0.1 g −1 K −1 at room temperature for pure graphite [38]. As fabrics are formed in biaxial stitched or woven structures, more air is incorporated in the structure of higher cp = 1 J g −1 K −1 [39] than graphite, increasing the overall cp value of the fabric. NCF300-biaxial has a cp varying from 0.67 J g −1 K −1 at 30 °C to 0.82 J g −1 K −1 at 138 °C (Figure 5c). According to the material specifications, the polyester stitch has a glass transition of 80 °C and melting point of 260-270 °C, and the binding agent has a melting point of 110 °C. No endothermic effects indicating glass transition of the stitch or melting of the binder are visible in the DSC curves, which may be due to the fact that the amount of binder (below 5 wt%) and stitch in the sample pan on the DSC instrument are negligible in their effect on heat flow.  The plain weave has a cp varying from 0.78 J g −1 K −1 at 30 °C to 1 J g −1 K −1 at 138 °C ( Figure 6a). The 4 × 4 twill weave has a cp varying from 0.57 J g −1 K −1 at 30 °C to 0.7 J g −1 K −1 at 125 °C (Figure 6b). The 5H satin weave has a cp varying from 0.75 J g −1 K −1 at 30 °C to 0.94 J g −1 K −1 at 138 °C (Figure 6c). The plain weave has a c p varying from 0.78 J g −1 K −1 at 30 • C to 1 J g −1 K −1 at 138 • C (Figure 6a). The 4 × 4 twill weave has a c p varying from 0.57 J g −1 K −1 at 30 • C to 0.7 J g −1 K −1 at 125 • C (Figure 6b). The 5H satin weave has a c p varying from 0.75 J g −1 K −1 at 30 • C to 0.94 J g −1 K −1 at 138 • C (Figure 6c).

Results of Thermal Conductivity
All results of thermal conductivity are summarized in Table 1. First of all, the analysis for the longitudinal thermal conductivity parallel to the fibers of one layer of NCF300biaxial is presented in Figure 7, with the X,Y axes of the plot defined by the relations in (3a). Triads of points were selected in the bottom ply as depicted in Figure 4b, where parallel horizontal fibers were facing the camera. The linear fit of Equation (3) in Figure 7 yields an elongational thermal diffusivity of 6.8 × 10 −6 m 2 s −1 , which after substituting the density and specific heat capacity values yields a value for the elongational thermal conductivity of NCF300-biaxial: k ll = 2.9 ± 0.4 W m −1 K −1 (standard error calculated from three repeat experiments). Taking the value of the axial thermal conductivity of T-300 carbon fibers as k f,a = 8.4 W m −1 K −1 [31,[39][40][41][42][43] and a measured V f = 0.35 (via burn off tests), the rule of mixtures yields a theoretically calculated k ll = 2.94 W m −1 K −1 , which is very close to the experimental value, also taking into account the experimental errors.

Results of Thermal Conductivity
All results of thermal conductivity are summarized in Table 1. First of all, the analysis for the longitudinal thermal conductivity parallel to the fibers of one layer of NCF300biaxial is presented in Figure 7, with the X,Y axes of the plot defined by the relations in (3a). Triads of points were selected in the bottom ply as depicted in Figure 4b, where parallel horizontal fibers were facing the camera. The linear fit of Equation (3) in Figure 7 yields an elongational thermal diffusivity of 6.8 × 10 -6 m 2 s −1 , which after substituting the density and specific heat capacity values yields a value for the elongational thermal conductivity of NCF300-biaxial: kll = 2.9 ± 0.4 W m −1 K −1 (standard error calculated from three repeat experiments). Taking the value of the axial thermal conductivity of T-300 carbon fibers as kf,a = 8.4 W m −1 K −1 [31,[39][40][41][42][43] and a measured Vf = 0.35 (via burn off tests), the rule of mixtures yields a theoretically calculated kll = 2.94 W m −1 K −1 , which is very close to the experimental value, also taking into account the experimental errors.  The next step is the determination of the transverse conductivity for all fabrics, the analysis of which is presented in Figure 8 and the results are presented in Table 1. Starting with NCF300-biaxial in Figure 8a, a transverse thermal diffusivity of 0.15 × 10 −6 m 2 s −1 is determined from the gradient of the linear data fit, yielding a thermal conductivity of kT = 70 ± 7 mW m −1 K −1 (standard error calculated from three repeat experiments). Employing Clayton's Equation (1) and substituting the values kf,a = 8.4 W m −1 K −1 [31,[39][40][41][42][43], kf,t = 0.84 W m −1 K −1 [31,40,44], and air as the matrix with km = 26-34 W m −1 K −1 in the temperature range of 30-140 o C [45], the theoretical value for the transverse conductivity of NCF300biaxial was found to be: kT = 63 mW m −1 K −1 . Comparing our thermal conductivity values to those of El-Hage et al. [33], our elongational conductivity is lower, but ours refers to one ply with fibers parallel to the face opposite the thermal camera. Considering that our total NCF300-biaxial is at 0/90 orientation, the overall in-plane conductivity is the average of kll and kT values (uncompressed), yielding 1.45 W m −1 K −1 , which is similar to that measured in the literature [33]. Our kT values are lower than El-Hage's et al. [33], where the latter found kT = 0.11 W m −1 K −1 for a six-layer NCF stack, but are closer to the theoretical values of Clayton's model than El-Hage's values. Furthermore, differences exist between NCFs The next step is the determination of the transverse conductivity for all fabrics, the analysis of which is presented in Figure 8 and the results are presented in Table 1. Starting with NCF300-biaxial in Figure 8a, a transverse thermal diffusivity of 0.15 × 10 −6 m 2 s −1 is determined from the gradient of the linear data fit, yielding a thermal conductivity of k T = 70 ± 7 mW m −1 K −1 (standard error calculated from three repeat experiments). Employing Clayton's Equation (1) and substituting the values k f,a = 8.4 W m −1 K −1 [31,[39][40][41][42][43], k f,t = 0.84 W m −1 K −1 [31,40,44], and air as the matrix with k m = 26-34 W m −1 K −1 in the temperature range of 30-140 • C [45], the theoretical value for the transverse conductivity of NCF300-biaxial was found to be: k T = 63 mW m −1 K −1 . Comparing our thermal conductivity values to those of El-Hage et al. [33], our elongational conductivity is lower, but ours refers to one ply with fibers parallel to the face opposite the thermal camera. Considering that our total NCF300-biaxial is at 0/90 orientation, the overall in-plane conductivity is the average of k ll and k T values (uncompressed), yielding 1.45 W m −1 K −1 , which is similar to that measured in the literature [33]. Our k T values are lower than El-Hage's et al. [33], where the latter found k T = 0.11 W m −1 K −1 for a six-layer NCF stack, but are closer to the theoretical values of Clayton's model than El-Hage's values. Furthermore, differences exist between NCFs with regard to the frequency and type of stitch, resulting in different size voids or eyelets at the locations of the stitch entering the fabric. Figure 8b presents the analysis for yielding the transverse thermal conductivity of the plain weave in this study determined as k T = 0.05 ± 0.02 W m −1 K −1 (standard error calculated from two repeat experiments), which is lower than that of the NCF300-biaxial and lower than the prediction of Clayton's model presented in Table 1 for an equivalent 0/90 • fabric with the same fiber fraction as the plain weave, V f = 0.42. It is clear that the large voids present at the yarn crossover points of the uncompressed plain weave (with such low V f ) result in low transverse thermal conductivity and create a gap between the experimental and theoretical values. Moreover, a large data scatter in relation to the linear fit is observed in Figure 8b compared to Figures 8a and 7 and a high experimental error between the repeat experiments is also observed. This scatter was also observed in the measurements of the thermal conductivity of thermoelectric fabrics using thermal maps [34] and attributed to the fact that the j − 1, j, and j + 1 numerical location points of the discretized Equation (3) were distributed in the mesoscopic scale of the fabric [46], hence, each point may be located in a macropore between yarns or inside a yarn or at other intermediate locations. So, the individual temperature measurements do not represent the composite cross-section as a continuum but individual components of the mesoscopic structure. Nevertheless, it is considered that the best fits through each dataset represent an average thermal conductivity for the continuum.
large voids present at the yarn crossover points of the uncompressed plain weave (with such low Vf) result in low transverse thermal conductivity and create a gap between the experimental and theoretical values. Moreover, a large data scatter in relation to the linear fit is observed in Figure 8b compared to Figures 8a and 7 and a high experimental error between the repeat experiments is also observed. This scatter was also observed in the measurements of the thermal conductivity of thermoelectric fabrics using thermal maps [34] and attributed to the fact that the j − 1, j, and j + 1 numerical location points of the discretized Equation (3) were distributed in the mesoscopic scale of the fabric [46], hence, each point may be located in a macropore between yarns or inside a yarn or at other intermediate locations. So, the individual temperature measurements do not represent the composite cross-section as a continuum but individual components of the mesoscopic structure. Nevertheless, it is considered that the best fits through each dataset represent an average thermal conductivity for the continuum.   Figure 8c presents the analysis for the 4 × 4 twill weave resulting in k T = 0.04 ± 0.02 W m −1 K −1 (standard error calculated from two repeat experiments), which is similar to the transverse thermal conductivity of the plain weave, given similar issues of void space in the loose crossover regions. It is also compared to a higher theoretical value of k T = 0.057 W m −1 K −1 for the 4 × 4 twill weave using Clayton's model (Table 1), the difference again being due to the lack of a detailed microstructural pattern in Clayton's model. The 5H satin weave (Figure 8d) had a surprisingly low transverse conductivity from the analysis of the temperature maps, k T = 0.004 ± 0.003 W m −1 K −1 (standard error calculated from two repeat experiments), which was confirmed from the analysis of the data from other triads of transverse locations in the fabric. The reason for this might be that the crossover pattern creates a much looser structure than an equivalent stitched fabric. In the case of the 5H satin weave, it seems that the long 0 • yarn regions over four 90 • yarns leave a long gap from the hot plate, which dramatically reduces the rate of heat conduction and, hence, the transverse thermal conductivity of the overall fabric.
It must also be noted that the heat conduction measurements were performed on a single layer of each fabric, in direct contact with the flat hot plate and the flat diaphragm, which leaves larger gaps compared to large stacks of fabrics which would benefit from the nesting of yarns and other microstructural features that would increase the overall number of contact points and contact area between individual fabric layers, yielding higher values of transverse thermal conductivity. Indeed, this was observed by El-Hage et al. [33] when they increased the number of fabric layers in the stack, especially when they secured the assembly with through-thickness stitching in 3D fabric architectures.

Conclusions
The heat transfer properties of single play fabrics were measured using DSC to determine the specific heat capacity and temperature maps from the video of an IR thermal imaging camera to determine the longitudinal (parallel to fiber) and transverse (though-thickness of fabric) thermal conductivity. DSC in the temperature range of 30-138 • C yielded c p values in the corresponding range of 1.3-1.4 J g −1 K −1 for silicone rubber (used as diaphragm material in preforming) and 0.12-0.25 J g −1 K −1 for the unidirectional carbon NCF, agreeing with the data in the literature [37,38]. Biaxial carbon woven fabrics exhibited higher c p values than the unidirectional NCF, in the corresponding range of 0.67-0.82 J g −1 K −1 for the NCF300-biaxial, 0.78-1 J g −1 K −1 for the plain weave, 0.57-0.7 J g −1 K −1 for the 4 × 4 twill weave, and 0.75-0.94 J g −1 K −1 for the 5H satin weave.
One may conclude that the novel technique of thermal map analysis is appropriate for the determination of the thermal diffusivity at the continuum level from the linear fit of the experimental data, even if there is considerable data scatter due to the discrete locations of the data points distributed in the mesoscopic scale of the fabric architecture where individual points might correspond to voids or particular features of the yarn or tow pattern. In particular, the determined value of the elongational thermal conductivity k ll = 2.9 ± 0.4 W m −1 K −1 of the NCF300-biaxial carbon fabric agreed well with the theoretical value calculated employing the rule of mixtures. The transverse thermal conductivity of the NCF300-biaxial carbon fabric is k T = 0.070 ± 0.007 W m −1 K −1 , 41 times lower than the elongational thermal conductivity following the same trend as the predictions of the theoretical modeling, where the Clayton model was employed for k T .
Comparing the different fabric architectures, the effect of voids due to yarn crossovers in woven fabrics was evident in the measured values of both c p and k T . A unidirectional NCF fabric exhibited the lowest c p value, close to that of pure graphite. The rest of the biaxial fabrics, NCF or woven, had higher c p values due to the air trapped in the voids of their structure. In terms of the measured transverse conductivity, all biaxial carbon fabrics, especially the woven fabrics that have more voids due to the yarn crossover regions, exhibited low thermal conductivity: 0.05 ± 0.02 W m −1 K −1 for the plain weave, 0.04 ± 0.02 0.04 ± 0.02 W m −1 K −1 for the 4 × 4 twill weave, and 0.004 ± 0.003 W m −1 K −1 for the 5H satin weave. This was attributed to the fact that they were all laid as single ply leaving large gaps between the fabric and the hot plate at or between the yarn crossover regions. It is also noticed that the percentage standard error in the repeat experiments to determine the transverse thermal conductivity is higher for the woven fabrics, 40-75%, than for the NCF-biaxial fabric, 10%. It is expected that stacks of fabrics would have higher transverse conductivity due to beneficial contributions from nesting effects. The Clayton model predictions of k T demonstrated the best agreement for the NCF300-biaxial fabric which contained the smallest number of voids under compression, especially between the flat surfaces of the hot plate and the rubber diaphragm.
Author Contributions: Conceptualization, P.K. and C.L.; methodology, P.K. and C.L.; validation, P.K., C.L. and S.B.; formal analysis, P.K.; investigation, P.K., C.L. and S.B.; resources, C.L. and S.B.; data curation, P.K. and C.L.; writing-original draft preparation, P.K.; writing-review and editing, P.K. and C.L.; visualization, P.K.; supervision, C.L. and S.B.; funding acquisition, C.L. and S.B. All authors have read and agreed to the published version of the manuscript. Data Availability Statement: Data will be made available after reasonable requests to the corresponding authors.