Mechanical Response and Processability of Wet-Laid Recycled Carbon Fiber PE, PA66 and PET Thermoplastic Composites

: The interest in recycled carbon ﬁber (rCF) is growing rapidly and the supply chain for these materials is gradually being established. However, the processing routes, material intermediates and properties of rCF composites are less understood for designers to adopt them into practice. This paper provides a practical pathway for rCFs in conjunction with low cost and, for the most part, commodity thermoplastic resins, namely polyethylene (PE), polyamide 66 (PA66) and polyethylene terephthalate (PET). Industrially relevant wet-laid (WL) process routes have been adopted to produce mats using two variants of WL mats, namely (a) high speed wet-laid inclined wire to produce broad good ‘roll’ forms and (b) 3DEP TM process patented by Materials Innovation Technologies (MIT)-recycled carbon ﬁber (RCF), now Carbon Conversions, which involves mixing ﬁbers and water and depositing the ﬁbers on a water-immersed mold. These are referred to as ‘sheet’ forms. The produced mats were evaluated for their processing into composites as ‘fully consolidated mats’ and ‘non-consolidated’ as-produced mats. Comprehensive mechanical data in terms of tensile strength, tensile modulus and impact toughness for rCF C/PE, C/PA66 and C/PET are presented. The work is of high value to sustainable composite designers and modelers.


Introduction
Discontinuous carbon fibers have a number of advantages, such as (a) fiber aspect ratio can be greater than critical fiber length, hence, superior mechanical properties can be realized; (b) higher drapeability offered due to fiber movement during processes, such as compression and thermo-stamping; (c) ability to hybridize fiber lengths and types; and (d) lower cost, since secondary weaving and braiding are not necessary. Traditional processes, such as injection molding and extrusion, result in significant fiber length attrition due to friction and interaction with the screw with the material. Wet-laid (WL) processing offers a low-energy alternative to traditional processes, such as weaving and/or stitch bonding, producing mats in desired fiber-matrix weight fraction. Both reinforcing fibers and resin fibers (resin in fiber form) are mixed in desired weight proportion in water (with dispersant and flocculent) and mixed till the material assumes a homogenous form. The water is drained rapidly from the fiber bulk, resulting in a well-dispersed fiber-polymer mat.
Two types of industrially relevant WL mat process routes have been investigated in this work, namely-(a) high speed wet-laid line to produce broad good 'roll' forms and (b) 3DEP TM process patented by Carbon Conversions, mixing fibers and water, and There are presently no systematic guidelines of using rCF in composite products. This paper attempts to address this gap, and addresses commodity and engineering thermoplastics with rCFs to provide a comprehensive understanding of lower-and upper-bound properties with these materials. The work is of high relevance to sustainable composite designers and end users.

Materials and Methods
Two WL-processing approaches were considered in this study. Nonwoven rCFthermoplastic mats were produced (a) in a WL machine capable of producing 'roll' forms; and (b) 3DEP TM process where rCF mats were deposited as a 'sheet' in a water tank. Throughout this manuscript these variants are referred to as 'roll' and 'sheet' forms, respectively.
The 'roll' mats were produced in 1.2 m (48") wide rolls, while the 'sheets' were produced as 3DEP TM mats using a water-based deposition on a screen tool. A 'sheet' was typically 350 mm × 350 mm WL mat.
'Sheet': Carbon Conversions developed an innovative method for making WL fiber preforms [5]. The 3DEP TM process lends itself to converting loose recycled fibers into nonwoven carbon fiber mats. The 3DEP TM process uses advanced slurry molding process for creating nonwoven rCF preforms. 3DEP TM produces homogeneous fiber distribution within the mat with consistent areal weight and acceptable dimensional tolerance. In this work 3DEP TM was used to produce WL rCF mats. rCF obtained from pyrolysis of T800 prepreg were used. The recycled fiber had nominal 12.7 mm fiber length and 8-10 mm diameter.
'Roll': Carbon Conversions produces continuous, WL, nonwoven fabrics on a 1.2 m wide RotoFormer machine (Allimand Interweb, Inc., Glen Falls, NY, USA). Compositions include chopped carbon fiber and blends of carbon fiber with thermoplastic polymer staple fibers. Areal density can range from 100 to 500 g/m 2 (gsm). Areal density coefficient of variation (COV) is typically <3%. After forming, the web is sent through a continuous dryer and then bound onto 50-200 m rolls. rCF mats were processed via WL with three resin systems: PE, PA66 and PET, respectively. The molecular weights are as follows: PET-25,000 g/mol, PE-30,000 g/mol and PA66-25,000 g/mol. The tensile modulus of neat (unreinforced) PET is 2.8 GPa, PE is 0.9 GPa and PA66 is 3.2 GPa, respectively.
The C/PET and C/PA66 were processable at 500 F due to their higher melting point, while PE was processed at 250 F since PE melts at a lower temperature. The work was conducted in two batches referred to as Batch 1 and Batch 2. The lessons from Batch 1 were applied in producing Batch 2 mats. Table 1 summarizes the rCF mats designed for the 'roll' and 'sheet' forms under Batch 1. Batch 2 mats are discussed later. Composite panels were made from the WL mats using compression-molding process with the process conditions identified in the table.

Partial and Fully Consolidated Panels
Compression molding was used to produce partially and fully consolidated panels as illustrated in Figure 1a-f. Five (5) layers of 300 mm × 300 mm preforms were compression molded in a matched metal tool. For C/PA66, the press platens were heated to a temperature of 500 • F at 6.895 MPa (1000 psi). In a few cases, the tool temperature was held at 250-265 • F. The hold time was approximately 20 min at temperature. The tool was cooled to room temperature. In some cases, slight discoloration was noted along the edges of the panel-12 mm wide band along the four edges.

Partial and Fully Consolidated Panels
Compression molding was used to produce partially and fully consolidated panels as illustrated in Figure 1a-f. Five (5) layers of 300 mm × 300 mm preforms were compression molded in a matched metal tool. For C/PA66, the press platens were heated to a temperature of 500 °F at 6.895 MPa (1000 psi). In a few cases, the tool temperature was held at 250-265 °F. The hold time was approximately 20 min at temperature. The tool was cooled to room temperature. In some cases, slight discoloration was noted along the edges of the panel-12 mm wide band along the four edges. The C/PE and C/PET panels were produced in a similar manner to C/PA66. Two panels of PE-CF-78-20 roll were processed as three layers of preforms were compression molded in a 300 × 300 mm matched metal tool. The tool was heated to a temperature of 250 °F (for C/PE) and 500 °F (for C/PET) at 6.895 MPa (1000 psi). The hold time was approximately 20 min at these temperatures. The tool was cooled to room temperature.

'Roll' versus 'Sheet' Forms
Preform "sheets" and "roll" forms were evaluated in similar weight fraction and resin type(s). For example, 'sheet(s)' PA66-CF-68-30 and PA66-CF-78-20 and 'roll' PA66-CF-77-20 (e.g., PA66-CF-77-20 means 77 wt% PA66 and 20 wt% CF) were evaluated and  The C/PE and C/PET panels were produced in a similar manner to C/PA66. Two panels of PE-CF-78-20 roll were processed as three layers of preforms were compression molded in a 300 × 300 mm matched metal tool. The tool was heated to a temperature of 250 • F (for C/PE) and 500 • F (for C/PET) at 6.895 MPa (1000 psi). The hold time was approximately 20 min at these temperatures. The tool was cooled to room temperature.

'Roll' versus 'Sheet' Forms
Preform "sheets" and "roll" forms were evaluated in similar weight fraction and resin type(s). For example, 'sheet(s)' PA66-CF-68-30 and PA66-CF-78-20 and 'roll' PA66-CF-77-20 (e.g., PA66-CF-77-20 means 77 wt% PA66 and 20 wt% CF) were evaluated and compared. Qualitatively, the 'roll' form processed under similar conditions consolidated better (less voids) than 'sheets'. Figure 2 illustrates a representative 'roll' and 'sheet' form composite panel. Moisture analysis revealed that the 'roll' form had less moisture content. The material was dried before consolidation. Parallel edge coupons were tabbed and tested in two (2) directions 'along' and 'across' the machine direction. The direction was more relevant in the 'roll' due to preferential fiber orientation along the warp (machine) direction. compared. Qualitatively, the 'roll' form processed under similar conditions consolidated better (less voids) than 'sheets'. Figure 2 illustrates a representative 'roll' and 'sheet' form composite panel. Moisture analysis revealed that the 'roll' form had less moisture content. The material was dried before consolidation. Parallel edge coupons were tabbed and tested in two (2) directions 'along' and 'across' the machine direction. The direction was more relevant in the 'roll' due to preferential fiber orientation along the warp (machine) direction.

Moisture Analysis
Moisture analysis was conducted to determine moisture content in the preform 'sheets and 'roll'. Percentage moisture was determined by weight analysis. The samples studied were PA66-CF-78-20 preform 'sheets' and PA66-CF-77-20 preform "roll". The materials were dried at 250 °F for 8 hrs. Table 2 illustrates the moisture percent in the 'sheet' versus 'roll' preform. The 'sheet' exhibited an average moisture content of 3% while the 'roll' exhibited average moisture of 1.68%, about 45% lower than the 'sheet'. Tension samples were cut from the consolidated 300 × 300 mm plate. Flat-wise tabs were used for the tension samples (25.4 mm wide and 200 mm length). Some dog bone samples were also tested in a couple of variants to observe the effect of sample shape and size of final properties. Strength and modulus were determined for three specimens each, 'along' and 'across' the fiber directions at a rate 2 mm/min. The modulus was determined with an extensometer (0.2% to 1 % strain).

Moisture Analysis
Moisture analysis was conducted to determine moisture content in the preform 'sheets and 'roll'. Percentage moisture was determined by weight analysis. The samples studied were PA66-CF-78-20 preform 'sheets' and PA66-CF-77-20 preform "roll". The materials were dried at 250 • F for 8 h. Table 2 illustrates the moisture percent in the 'sheet' versus 'roll' preform. The 'sheet' exhibited an average moisture content of 3% while the 'roll' exhibited average moisture of 1.68%, about 45% lower than the 'sheet'. Tension samples were cut from the consolidated 300 × 300 mm 2 plate. Flat-wise tabs were used for the tension samples (25.4 mm wide and 200 mm length). Some dog bone samples were also tested in a couple of variants to observe the effect of sample shape and size of final properties. Strength and modulus were determined for three specimens each, 'along' and 'across' the fiber directions at a rate 2 mm/min. The modulus was determined with an extensometer (0.2% to 1 % strain).

Batch 1 Results
Tables 3 and 4 summarize the tensile modulus and strength for composites made with C/PA66 'sheets' versus 'roll', respectively. It is seen that the C/PA66 'roll' had 67% higher average tensile strength (108 MPa ('sheet') versus 187.73 MPa ('roll')) and 72% higher average modulus (10 GPa ('sheet') versus 16.5 GPa ('roll')). The high values for the 'roll' can be attributed to the preferential fiber alignment in the 'roll' direction while the 'sheet' exhibits quasi-isotropic/random orientation. There was no statistical difference in the tensile strength and modulus between the flat edge specimens compared to the dog bone specimen geometry as shown in Table 5.
The 30 wt% C/PE 'roll' specimens exhibited an average tensile strength of 45 MPa and tensile modulus of 6.5 GPa. These were approximately half that of the 30 wt% C/PA66 composites. The C/PE was only tested (available) in the 'roll' direction.

Batch 2 Results-Tensile Modulus and Tensile Strength
Based on the results from Batch 1, a controlled set of preforms was prepared with approximately 20 wt% CF for PA66, PE and PET, respectively. Composite plates were produced in two configurations, namely, 'no cross-stack' and 'cross-stack', respectively. The rationale for the two configurations was to evaluate if the preferential fiber orientation in the 'roll' influenced the stacking sequence.
Tables 6-8 summarize the results from these materials. The trend of the 'roll' form of higher values than the 'sheet' forms was similar to that in Batch 1. The 'roll' form had 88% higher strength and 137% higher modulus compared to the 'sheet' form. This indicates the influence of significant fiber orientation in the 'roll' form. The effect of drying the mats in Batch 2 had a marked influence in the 'sheet' form. Drying improved the tensile strength and modulus by an average factor of two or greater. Batch 2 of the PE/CF panels was processed at a higher temperature than Batch 1 (260 • F instead of 245 • F). Increasing the processing temperature increased the tensile strength marginally. The cross-stack panel exhibits similar properties in both the directions while the no-cross stack exhibits a difference in properties in the two directions as shown in Table 9. C/PET sheet preforms were processed at 500 F and 100 psi. These exhibit excellent tensile modulus and strength and are comparable to the C/PA66 samples. Table 10 compares the density of the mats for different weight fractions for C/PA66, C/PET and C/PE, respectively. The C/PA66 composite density ranged from 1.18 and 1.21 to 1.24 g/cc for 10%, 20% and 30 wt%, respectively. The C/PE was 1.03 and C/PET 1.42 g/cc for 20 wt%, respectively. The densest of the materials was C/PET. Table 11 summarizes typical (standard) materials, such as aluminum, ABS and long glass fiber thermoplastics, for comparison to the carbon fiber mats in terms of the density, strength and modulus, respectively. Table 12 provides a detailed summary of all material variants studied in this work C/PA66, C/PE and C/PET for 'roll' and 'sheet' forms in no-stack and cross-stack configurations, where applicable. The data are summarized in terms of density, strength, modulus, specific strength and specific modulus.

Low-Velocity Impact Testing
The specimens were subjected to drop tower impact on a Dynatup 8250 under clamped plates 100 × 100 mm with drop height impact for two energy levels (5 J and 15 J) (or drop heights), referred to as 'low-energy 5 J' and 'high-energy 15 J' impact. Tables 13 and 14 summarized the impact data for all variants tested for drop weight impact. Figures 3 and 4 compares the normalized load and normalized energy for variants of 20 wt% carbon fiber in each of C/PA66, C/PET and C/PE for no-stack versus cross-stack, where applicable.     At lower energy, the highest peak loads attained were from C/PE and C/PET, respectively. In both these systems, once the peak on the force-time curve was attained, there was penetration of the impactor through the thickness, and the unloading was, hence, sudden. While the normalized energy was highest for C/PA66, both no-stack and crossstack compared to the rest. This suggests that C/PA66-exhibited-energy absorption occurs both in the loading and unloading phase. There is no penetration of the indenter for C/PA66. For higher energy impact, C/PA66 and C/PET exhibited the highest normalized load bearing for the cross-stack. The highest energy absorbed was noted for all C/PE variants, regardless of no-stack or cross-stack.
The effect of stacking was less pronounced in all the impact tested samples. This may be due to localized transverse impact and only limited contact area between the impactor and the specimen. Cross-stack or no-stack is more of a function for in-plane loading. The peak load in case of drop weight impact is the onset at which the unloading phase begins. Energy absorption continues into the unloading phase for damage-tolerant materials. Overall, the PA66 offered higher damage tolerance in terms of energy absorption, for both low-and high-energy impact.

Discussion
Figures 5-7 provide a comprehensive visual of all tests conducted for C/PA66, C/PE and C/PET, respectively. Where applicable, the no-stack versus cross-stack has been reported. The overall tensile strength of 'roll' form of C/PA65 ranged from 217 to 248 MPa and tensile modulus of 15-20 GPa, respectively. The differences between cross-stack and no-stack are not very definitive, indicating fiber entanglement occurs in discontinuous fibers, masking the distinct effect of fiber orientation. In some cases, modulus and strength for cross-stack were lower by 12.5% compared to no-stack.
For 77 wt % C/PET (i.e., 23% CF), the highest values of strength ranged from 243 to 271 MPa and modulus 16-17 GPa for the 'sheet' form. For the 'roll' form, there was a distinct difference in the cross-stack versus no-stack, or high anisotropy. The values ranged from 128 to 170 MPa and modulus of 5-10 GPa, much lower than other variants. Further, the fiber content in these was only 15 wt%, unlike the others, which were >20 wt% At lower energy, the highest peak loads attained were from C/PE and C/PET, respectively. In both these systems, once the peak on the force-time curve was attained, there was penetration of the impactor through the thickness, and the unloading was, hence, sudden. While the normalized energy was highest for C/PA66, both no-stack and cross-stack compared to the rest. This suggests that C/PA66-exhibited-energy absorption occurs both in the loading and unloading phase. There is no penetration of the indenter for C/PA66. For higher energy impact, C/PA66 and C/PET exhibited the highest normalized load bearing for the cross-stack. The highest energy absorbed was noted for all C/PE variants, regardless of no-stack or cross-stack.
The effect of stacking was less pronounced in all the impact tested samples. This may be due to localized transverse impact and only limited contact area between the impactor and the specimen. Cross-stack or no-stack is more of a function for in-plane loading. The peak load in case of drop weight impact is the onset at which the unloading phase begins. Energy absorption continues into the unloading phase for damage-tolerant materials. Overall, the PA66 offered higher damage tolerance in terms of energy absorption, for both low-and high-energy impact.

Discussion
Figures 5-7 provide a comprehensive visual of all tests conducted for C/PA66, C/PE and C/PET, respectively. Where applicable, the no-stack versus cross-stack has been reported. The overall tensile strength of 'roll' form of C/PA65 ranged from 217 to 248 MPa and tensile modulus of 15-20 GPa, respectively. The differences between cross-stack and no-stack are not very definitive, indicating fiber entanglement occurs in discontinuous fibers, masking the distinct effect of fiber orientation. In some cases, modulus and strength for cross-stack were lower by 12.5% compared to no-stack.
For 77 wt% C/PET (i.e., 23% CF), the highest values of strength ranged from 243 to 271 MPa and modulus 16-17 GPa for the 'sheet' form. For the 'roll' form, there was a distinct difference in the cross-stack versus no-stack, or high anisotropy. The values ranged from 128 to 170 MPa and modulus of 5-10 GPa, much lower than other variants. Further, the fiber content in these was only 15 wt%, unlike the others, which were >20 wt% carbon fiber. It may also be noted for the no-stack roll form, when a high degree of fiber orientation in the machine direction occurs, the strength and modulus are high, i.e., 256 MPa and 16 GPa, respectively.
The 77 wt% C/PE (i.e.,~20 wt% carbon fiber) exhibited the lowest values of all. For cross-stack, the average modulus was 53 MPa and average strength was 5.5 GPa, similar in both directions for cross-stack. For the no-cross stack, significant anisotropy was observed at 39 and 66 MPa and 4 and 6 GPa modulus. Figure 8 considers a long fiber thermoplastic C/PPS with 40 wt% 25 mm (1") fiber length, which has strength of 175 MPa and modulus 25 GPa. Although this is not a one-toone comparison, both C/PA66 and C/PET rCF mat composites have much higher modulus (by 37 %), higher than LFT C/PPS. The strength of C/PPS was 25% higher, the C/PA66 rCF mats providing the closest to the LFT values. carbon fiber. It may also be noted for the no-stack roll form, when a high degree of fiber orientation in the machine direction occurs, the strength and modulus are high, i.e., 256 MPa and 16 GPa, respectively.
The 77 wt% C/PE (i.e., ~20 wt% carbon fiber) exhibited the lowest values of all. For cross-stack, the average modulus was 53 MPa and average strength was 5.5 GPa, similar in both directions for cross-stack. For the no-cross stack, significant anisotropy was observed at 39 and 66 MPa and 4 and 6 GPa modulus. Figure 8 considers a long fiber thermoplastic C/PPS with 40wt% 25 mm (1") fiber length, which has strength of 175 MPa and modulus 25 GPa. Although this is not a oneto-one comparison, both C/PA66 and C/PET rCF mat composites have much higher modulus (by 37 %), higher than LFT C/PPS. The strength of C/PPS was 25% higher, the C/PA66 rCF mats providing the closest to the LFT values.   carbon fiber. It may also be noted for the no-stack roll form, when a high degree of fiber orientation in the machine direction occurs, the strength and modulus are high, i.e., 256 MPa and 16 GPa, respectively.
The 77 wt% C/PE (i.e., ~20 wt% carbon fiber) exhibited the lowest values of all. For cross-stack, the average modulus was 53 MPa and average strength was 5.5 GPa, similar in both directions for cross-stack. For the no-cross stack, significant anisotropy was observed at 39 and 66 MPa and 4 and 6 GPa modulus. Figure 8 considers a long fiber thermoplastic C/PPS with 40wt% 25 mm (1") fiber length, which has strength of 175 MPa and modulus 25 GPa. Although this is not a oneto-one comparison, both C/PA66 and C/PET rCF mat composites have much higher modulus (by 37 %), higher than LFT C/PPS. The strength of C/PPS was 25% higher, the C/PA66 rCF mats providing the closest to the LFT values.

Processing Studies
Optimal processing results were obtained from panels produced with tool temperature at 500 °F. The panels processed at 250-265 F tool temperature exhibited voids, as seen in Figure 1a,b. All panels used for testing were, hence, processed at 500 °F tool temperature. Several processing routes were attempted from the rCF mats.
(a) Compression molding of the preform in matched metal tool produced composite plates. The compression molding of the PA66 rCF mats was conducted to different consolidation pressures. This helped understand process temperature-pressure-

Processing Studies
Optimal processing results were obtained from panels produced with tool temperature at 500 °F. The panels processed at 250-265 F tool temperature exhibited voids, as seen in Figure 1a,b. All panels used for testing were, hence, processed at 500 °F tool temperature. Several processing routes were attempted from the rCF mats.
(a) Compression molding of the preform in matched metal tool produced composite plates. The compression molding of the PA66 rCF mats was conducted to different consolidation pressures. This helped understand process temperature-pressure-

Processing Studies
Optimal processing results were obtained from panels produced with tool temperature at 500 • F. The panels processed at 250-265 F tool temperature exhibited voids, as seen in Figure 1a,b. All panels used for testing were, hence, processed at 500 • F tool temperature. Several processing routes were attempted from the rCF mats.
(a) Compression molding of the preform in matched metal tool produced composite plates. The compression molding of the PA66 rCF mats was conducted to different consoli-dation pressures. This helped understand process temperature-pressure-microstructure relationships. The fully consolidated panels were used for mechanical testing/data generation; (b) compression molding of C/PA66 panels followed by pre-heating the consolidated panel and subsequently subjecting the heated panel to single-diaphragm thermoform (SDF), and (c) pre-heating the C/PA66 mats without compression molding (hence, a less stiff mat) and subjecting it to SDF.

Single-Diaphragm Forming of Pre-Consolidated Panel
The purpose of this study was to evaluate the formability of the mat(s) in terms of draw. PA66/CF/78/20 was consolidated using the 300 × 300 mm 2 tool for a 2.5 mm thick panel at 500 • F and 6.895 MPa (1000 psi). The consolidated panel (blank) was then re-heated in a convection oven for approximately 5 min at 490-500 • F. There was very little sag (if any) evident. A toy car mold (250 × 100 × 125 mm 3 ) was used as a tool to thermoform the consolidated blank. The blank exhibited some discoloration inside the oven. The blank was unable to soften and did not reach the melt temperature without degradation. As such, one atmosphere vacuum was used to form the part. The consolidated blank failed catastrophically during forming, as seen in Figure 9.
Compos. Sci. 2022, 6, x FOR PEER REVIEW 14 of 18 microstructure relationships. The fully consolidated panels were used for mechanical testing/data generation; (b) compression molding of C/PA66 panels followed by pre-heating the consolidated panel and subsequently subjecting the heated panel to single-diaphragm thermoform (SDF), and (c) pre-heating the C/PA66 mats without compression molding (hence, a less stiff mat) and subjecting it to SDF.

Single-Diaphragm Forming of Pre-Consolidated Panel
The purpose of this study was to evaluate the formability of the mat(s) in terms of draw. PA66/CF/78/20 was consolidated using the 300 × 300 mm tool for a 2.5 mm thick panel at 500 °F and 6.895 MPa (1000 psi). The consolidated panel (blank) was then reheated in a convection oven for approximately 5 min at 490-500 °F. There was very little sag (if any) evident. A toy car mold (250 × 100 × 125 mm) was used as a tool to thermoform the consolidated blank. The blank exhibited some discoloration inside the oven. The blank was unable to soften and did not reach the melt temperature without degradation. As such, one atmosphere vacuum was used to form the part. The consolidated blank failed catastrophically during forming, as seen in Figure 9. . Pre-consolidated blank (after heating and thermoforming). Sample-PA66/CF/78/20, 5 layers of preform; (a) exposed side in oven shows much yellowing; (b) non-exposed side shows less yellowing.
The pre-consolidated C/PA66 plate did not sag, hence, the plate was stiff when transferred from the oven to the forming station. Due to this, it appears that well-consolidated plates possess limited ability to form to shape, resulting in cracking in the C/PA66 resin. It appears that heating of the preforms must be done in a vacuum oven/inert condition to prevent discoloration (yellowing). Whether the yellowing is from moisture remains unclear. To find the cause for discoloration when the PA66/CF is heated in an oven, the preform was heated under vacuum or inert atmosphere to determine if discoloration occurs due to the presence of air, as shown in Table 15.  (a) exposed side in oven shows much yellowing; (b) non-exposed side shows less yellowing.
The pre-consolidated C/PA66 plate did not sag, hence, the plate was stiff when transferred from the oven to the forming station. Due to this, it appears that well-consolidated plates possess limited ability to form to shape, resulting in cracking in the C/PA66 resin. It appears that heating of the preforms must be done in a vacuum oven/inert condition to prevent discoloration (yellowing). Whether the yellowing is from moisture remains unclear. To find the cause for discoloration when the PA66/CF is heated in an oven, the preform was heated under vacuum or inert atmosphere to determine if discoloration occurs due to the presence of air, as shown in Table 15.

Compression Molding-External Heating (Heating the Preforms in a Convection Oven)
Two layers of PA66/CF/88/10 were placed in a convection oven at 500 • F for 5 min. A heated mold (with oil heating up to 350 • F) was used to compression mold the heated preforms. The blanks exhibited some discoloration inside the oven, see Figure 10a,b. Only the top layers of the preform became discolored due to heat. The bottom did not reach the processing temperature, nor did it discolor. Further, 1000 psi of positive pressure was applied on the tool.

Compression Molding-External Heating (Heating the Preforms in a Convection Oven)
Two layers of PA66/CF/88/10 were placed in a convection oven at 500 °F for 5 min. A heated mold (with oil heating up to 350 °F) was used to compression mold the heated preforms. The blanks exhibited some discoloration inside the oven, see Figure 10a,b. Only the top layers of the preform became discolored due to heat. The bottom did not reach the processing temperature, nor did it discolor. Further, 1000 psi of positive pressure was applied on the tool.

Single-Diaphragm Forming-PE/CF
One layer of PE-CF-78-20 was heated in an oven at 350 F for 5-6 min. The heated preform was transferred to the mold and subjected to one atmosphere of vacuum. The material formed well without any discoloration, see Figure 11.

Compression Molding-External Heating (Heating the Preforms in a Convection Oven)
Two layers of PE/CF/78/20 were heated in a convection oven at 400 °F for 10 min. An in-house heated mold (with oil heating at 250 °F) was used as a tool to compression mold the heated preforms. There was "no" discoloration of the blank inside the oven, see Figure  12a,b. Subsequently, 6.895 MPa (1000 psi) of positive pressure was applied on the tool.

Single-Diaphragm Forming-PE/CF
One layer of PE-CF-78-20 was heated in an oven at 350 F for 5-6 min. The heated preform was transferred to the mold and subjected to one atmosphere of vacuum. The material formed well without any discoloration, see Figure 11.

Compression Molding-External Heating (Heating the Preforms in a Convection Oven)
Two layers of PA66/CF/88/10 were placed in a convection oven at 500 °F for 5 min. A heated mold (with oil heating up to 350 °F) was used to compression mold the heated preforms. The blanks exhibited some discoloration inside the oven, see Figure 10a,b. Only the top layers of the preform became discolored due to heat. The bottom did not reach the processing temperature, nor did it discolor. Further, 1000 psi of positive pressure was applied on the tool.

Single-Diaphragm Forming-PE/CF
One layer of PE-CF-78-20 was heated in an oven at 350 F for 5-6 min. The heated preform was transferred to the mold and subjected to one atmosphere of vacuum. The material formed well without any discoloration, see Figure 11.

Compression Molding-External Heating (Heating the Preforms in a Convection Oven)
Two layers of PE/CF/78/20 were heated in a convection oven at 400 °F for 10 min. An in-house heated mold (with oil heating at 250 °F) was used as a tool to compression mold the heated preforms. There was "no" discoloration of the blank inside the oven, see Figure  12a,b. Subsequently, 6.895 MPa (1000 psi) of positive pressure was applied on the tool. Figure 11. Forming via SDF exhibited optimal draw and consolidation.

Compression Molding-External Heating (Heating the Preforms in a Convection Oven)
Two layers of PE/CF/78/20 were heated in a convection oven at 400 • F for 10 min. An in-house heated mold (with oil heating at 250 • F) was used as a tool to compression mold the heated preforms. There was "no" discoloration of the blank inside the oven, see Figure 12a

Discussion on Heating the Mats
Since the mats have significant open porosity and air (before consolidation), getting the mats to attain their processing temperature is important. Hence, pre-heating brings the mats to a uniform temperature and assists with the processing. It was observed that prior to consolidation, uniform heating of the mats, either in infrared oven or via contact heating in the closed-cavity, brings the mats to a processable condition. While the mechanical properties are more a function of optimal temperature and consolidation pressure, the efficient way to get to these conditions is via pre-heating to minimize time in the press (hence, higher process efficiency).

Conclusions
rCF WL mats were successfully produced in three resin types-PA66, PE and PET. The processing method had significant influence on properties. The 'sheet' form exhibited random/quasi-isotropic properties while the properties in the 'roll' form were guided by the preferred fiber orientation. The tensile strength and modulus were 80-120% higher on average in the 'roll' form compared to the 'sheet' form.
The tensile strength and modulus of the 77 wt% resin, ~20 wt% fiber mats ranked as C/PA66 > C/PET > C/PE guided by the resin properties. Some variants, such as C/PE 20 wt% carbon fiber, had higher anisotropy, i.e., they were more sensitive for the cross-stack versus no-stack, while in some variants, the fiber entanglement seems to minimize the influence of fiber orientation, i.e., differences in properties in the no-stack versus crossstack were less discernable.
The impact response of the rCF mats indicated the best performance came from C/PA66, while the energy absorbed by C/PE is assumed to be the highest, due to the weaker bonding between C and PE; as evident from the strength and modulus, this helps with energy absorption.
For PA66-CF, pre-drying was an important step as it influenced the properties by a factor of 2 or greater; pre-dried mats performed higher. The formability of pre-consolidated WL composites was poor due to high stiffness. Matched metal die provided the best forming of the WL mats for all the resin systems. The material loses heat rapidly, hence, the forming must be conducted immediately to pre-heating. The best formability was achieved in the PE-CF mats.
* Notice of Copyright: This manuscript has been authored by UT-Battelle, LLC under Contract No. DE-AC05-00OR22725 with the U.S. Department of Energy. The United States Government retains and the publisher, by accepting the article for publication, acknowledges that the United States Government retains a non-exclusive, paid-up, irrevocable, world-wide license to publish or reproduce the published form of this manuscript, or allow others to do so, for United States Government purposes. The Department of Energy will provide public access to these results of federally sponsored research in accordance

Discussion on Heating the Mats
Since the mats have significant open porosity and air (before consolidation), getting the mats to attain their processing temperature is important. Hence, pre-heating brings the mats to a uniform temperature and assists with the processing. It was observed that prior to consolidation, uniform heating of the mats, either in infrared oven or via contact heating in the closed-cavity, brings the mats to a processable condition. While the mechanical properties are more a function of optimal temperature and consolidation pressure, the efficient way to get to these conditions is via pre-heating to minimize time in the press (hence, higher process efficiency).

Conclusions
rCF WL mats were successfully produced in three resin types-PA66, PE and PET. The processing method had significant influence on properties. The 'sheet' form exhibited random/quasi-isotropic properties while the properties in the 'roll' form were guided by the preferred fiber orientation. The tensile strength and modulus were 80-120% higher on average in the 'roll' form compared to the 'sheet' form.
The tensile strength and modulus of the 77 wt% resin,~20 wt% fiber mats ranked as C/PA66 > C/PET > C/PE guided by the resin properties. Some variants, such as C/PE 20 wt% carbon fiber, had higher anisotropy, i.e., they were more sensitive for the cross-stack versus no-stack, while in some variants, the fiber entanglement seems to minimize the influence of fiber orientation, i.e., differences in properties in the no-stack versus cross-stack were less discernable.
The impact response of the rCF mats indicated the best performance came from C/PA66, while the energy absorbed by C/PE is assumed to be the highest, due to the weaker bonding between C and PE; as evident from the strength and modulus, this helps with energy absorption.
For PA66-CF, pre-drying was an important step as it influenced the properties by a factor of 2 or greater; pre-dried mats performed higher. The formability of pre-consolidated WL composites was poor due to high stiffness. Matched metal die provided the best forming of the WL mats for all the resin systems. The material loses heat rapidly, hence, the forming must be conducted immediately to pre-heating. The best formability was achieved in the PE-CF mats.
* Notice of Copyright: This manuscript has been authored by UT-Battelle, LLC under Contract No. DE-AC05-00OR22725 with the U.S. Department of Energy. The United States Government retains and the publisher, by accepting the article for publication, acknowledges that the United States Government retains a non-exclusive, paid-up, irrevocable, world-wide license to publish or reproduce the published form of this manuscript, or allow others to do so, for United States Government purposes. The Department of Energy will provide public access to these results of federally sponsored research in accordance with the DOE Public Access Plan (http://energy.gov/downloads/doe-public-access-plan) (accessed on 15 June 2022).