| HS Code | 518211 |
| Density | 1.35 g/cm³ |
| Tensile Modulus | 45 GPa |
| Tensile Strength | 450 MPa |
| Elongation At Break | 1.2% |
| Flexural Modulus | 42 GPa |
| Flexural Strength | 600 MPa |
| Charpy Impact Notched | 70 kJ/m² |
| Charpy Impact Unnotched | 210 kJ/m² |
| Heat Deflection Temperature 1 8 Mpa | 170 °C |
| Melting Temperature | 178 °C |
| Water Absorption 24h | 0.03% |
| Carbon Fiber Content | 59 wt% (45 vol%) |
As an accredited Envalior Tepex Dynalite 206-C200(x)/45% PA12-CF59, Dry factory, we enforce strict quality protocols—every batch undergoes rigorous testing to ensure consistent efficacy and safety standards.
| Packing | 25 kg dry, vacuum-sealed in moisture-barrier foil bags with desiccant, then packed in sturdy cardboard boxes for safe transport. |
| Container Loading (20′ FCL) | 20′ FCL: Dry PA12-CF59 composite pellets loaded into a standard 20-foot container, securely packed and ventilated for safe transport. |
| Shipping | Envalior Tepex Dynalite 206-C200(x)/45% PA12-CF59 is a dry, carbon-fiber-reinforced polyamide-12 composite laminate. Ship in sealed, moisture-proof packaging to prevent water absorption. Store flat, away from heat and ignition sources. Handle with care to avoid edge damage. No special dangerous-goods classification required under standard dry handling conditions. |
| Storage | Store Envalior Tepex Dynalite in its sealed, original packaging to prevent moisture absorption, as PA12 is hygroscopic. Keep in a cool, dry, well-ventilated area away from direct sunlight, heat sources, and humidity. Maintain temperatures below 30°C. Use dry desiccants if needed. Following these conditions preserves mechanical performance and ensures optimal processing. |
| Shelf Life | Store dry in original sealed packaging, away from moisture and heat. Shelf life is typically unlimited under proper storage conditions. |
Carbon-reinforced polyamide 12 ankle-foot orthoses are produced from multi-layer blanks of Envalior Tepex Dynalite 206-C200(x)/45% PA12-CF59 Dry because the continuous carbon fabric crosses the ankle hinge region and the calcaneal shelf as one uninterrupted ply, eliminating the short-fibre weld planes present in injection-moulded polyamide 12 parts. A production-scale far-infrared tunnel fitted with 2×600 W medium-wave emitters raises the laminate surface to 250–270°C while the core, monitored by an embedded thermocouple in the cold blank, reaches 220–240°C. Transfer time from the heating station to a matched aluminium mould is held below 5 s; closing is performed with a 100 t hydraulic press at 20–50 bar cavity pressure. Tool temperature is maintained at 80–110°C through oil-circulating channels because PA12 crystallises rapidly below 120°C and loses dimensional tolerance if the tool is colder. The 45% fibre volume fraction gives high bending stiffness but limits drape into small-radius features; radii below 2.0 mm on the mould cause fibre bridging and resin-starved corners. Cycle times of 45–90 s per part are typical when the sheet thickness is 1.0–2.0 mm. After demoulding, the parts are trimmed with polycrystalline diamond routers; feed rates above 1500 mm/min at 20,000 rpm produce edge delamination because of heat build-up. The material is tested for flexural strength and modulus according to ISO 14125:1998/Amd.1:2011 after conditioning at 23°C and 50% RH for 48 h. Because the PA12 matrix absorbs approximately 0.8% moisture at saturation under ISO 62:2008, wet-flexural modulus retention in orthotic service is higher than for PA6 matrices. Fatigue of finished constructions is evaluated under ISO 10328:2016 P5 loading; published comparative data for this specific Tepex grade in ISO 22523:2006 orthotic configurations remains limited. Failure in clinical service commonly appears as matrix microcracking at dorsal strap slot edges rather than fibre breakage, which is why trim edges are sealed with a 0.1–0.2 mm fillet of unfilled PA12 adhesive film before final assembly. The Dry designation means the sheet is supplied below 0.1% moisture; re-drying at 80°C for 2 h is performed if open exposure at more than 60% RH exceeds 4 h.
The component that most strongly controls cycle time in a racing seat shell is the transition from consolidation of the layup to overmoulded rib formation at the shell boundary. A blank heated to 250–270°C retains formability for 20–30 s once removed from an IR field; if a rib is injection-moulded as a second stage, the residual heat in the formed shell determines whether the overmoulded PA12 reaches the 175–180°C crystalline melting peak. Mould temperature is typically 90–120°C; below 90°C the overmoulded polyamide 12 freezes before full penetration into the boundary layer, and above 120°C ejection marks appear on visible carbon surfaces. In motorsport applications the formed shell is tested under ECE R17.06 for seat anchorage and FIA 8855-1999 for geometry and dynamic performance; flammability is assessed with ISO 3795:1989 and is normally reported as HB for unreinforced edges. Continuous-fibre swatch panels cut at 0°/90° fabric orientation give in-plane tensile modulus values that are substantially higher than short-fibre PA12 injection grades tested under ISO 527-4:2023, but published data for the specific 206-C200(x) architecture in straight seat-back bending are limited. The main production bottleneck is not heating but vacuum-assisted blank flattening: if the preheated blank sags more than 15 mm before the tool closes, fibre buckling appears at the shoulder harness slots. Therefore, the blank is supported by a vacuum gripper array that holds the sheet flat without masking more than 20% of the emitter area. One incompatibility observed on production lines is the use of PA66 overmoulding grades requiring melt temperatures above 285°C; this degrades the PA12 matrix at the interface. Only PA12 or PA11 overmould grades are used for the rib structure.
| Parameter | Value / range | Equipment / method |
|---|---|---|
| Surface heating temperature | 250–270°C | Medium-wave IR field, thermocouple-controlled |
| Core target temperature | 220–240°C | Embedded thermocouple in blank |
| Mould temperature | 80–120°C | Oil-circulating matched aluminium tool |
| Forming pressure | 20–50 bar | Hydraulic compression press |
| Transfer time | ≤5 s | Vacuum-assisted needle gripper |
| Typical part thickness | 1.0–2.0 mm | Single or double ply |
During airframe component manufacture, preforms are nested from a 1.2 m × 2.4 m sheet using a 100 W CO₂ laser cutter; the carbon fabric absorbs far-infrared energy efficiently and the PA12 matrix produces a narrow heat-affected zone if the assist gas is nitrogen and the cutting speed is kept above 800 mm/min. For fixed-wing UAV spar caps, the continuous carbon fabric path from root to tip gives a structural member that can be bonded into a foam-core wing with a methacrylate adhesive after flame treatment. Testing follows ASTM D3039/D3039M-17 for tensile strength and modulus of the consolidated laminate; published values for similar consolidated PA12-carbon fabric laminates are typically in the range of 500–700 MPa tensile strength, while compression-after-impact panels tested under ASTM D7136/D7136M-20 show retained compressive strength that depends heavily on impact energy and impactor diameter. When aluminium inserts are bolted through the laminate, a 0.25 mm glass-fibre insulation ply is placed under the carbon face to prevent galvanic corrosion; direct contact with copper alloy bushings is avoided because pitting appears after 500 h in salt spray per ISO 9227:2022. Stainless steel or titanium fasteners are used at the spar root and landing skid plate interfaces. In production, edge sealing after laser cutting is performed with a thin PA12 film to prevent moisture ingress and to eliminate carbon-fibre slivers that can create electrical shorting in the airframe electronics bay. Published data for this exact Tepex configuration in full UAV airframe bending fatigue are limited; coupon-level dynamic mechanical analysis is therefore used to establish allowable strain before design freeze.
Replacement of a 6061-T6 aluminium gripper jaw with a Tepex Dynalite 206-C200(x)/45% PA12-CF59 part begins with stiffness-to-mass calculation, not with direct geometry copy. The anisotropic laminate is specified so that the principal bending load along the jaw length coincides with the 0° fabric direction. Waterjet cutting with 0.3 mm garnet abrasive at 3000 bar leaves an edge with exposed carbon filaments; these edges are sealed with a thin PA12 film to prevent moisture ingress and electrical shorting in automated assembly cells. Fastener holes are drilled with diamond-coated bits at 12,000–18,000 rpm and 0.05 mm/rev feed; countersinking is done before forming, not after, because local delamination around the countersink appears when the laminate is rigid. The cut blank is thermoformed in a short-stroke press with tool temperature 100°C and cavity pressure 30 bar. Final deflection under a 500 N tip load is evaluated by ISO 14126:1999 in-plane compression and by ASTM D5961/D5961M-23 bearing strength. In a production-scale material handling line, aluminium jaws reached replacement after 1×10⁷ cycles from bearing elongation; the PA12-carbon jaws show lower mass but require bolt torque limiting to 4–6 N·m because bearing stress above the clamping limit induces creep in the thermoplastic matrix. Published cyclic bearing data for this exact laminate configuration is limited; end-users run coupon-level bearing fatigue programs before committing to field deployment. Overmoulding of a PA12 gripper pad at 90°C tool temperature improves grip without softening the carbon body because the short-cycle overmoulding step remains below the heat-deflection temperature of the consolidated laminate.
Radiolucent table shells fabricated from the PA12 carbon fibre grade are used where a structural panel must support patient mass while producing lower X-ray attenuation than aluminium. The thermoformed shell is typically 1.5 mm thick with a foam core, and the PA12 matrix avoids the moisture-induced dimensional changes seen in PA6 counterparts under repeated disinfectant exposure. The shell is formed, then bonded with a radiolucent structural adhesive to a polymethacrylimide foam core; the final assembly is tested for static load capacity under IEC 60601-1:2005+AMD1:2012 clause 9.8.2 mechanical strength. The carbon fabric itself is not completely radio-transparent; thin-walled sections of 1.0 mm produce a low but measurable attenuation that is eliminated in the region of interest by localised incorporation of aramid or glass-fibre plies. Because continuous carbon fibre is electrically conductive, any closed-loop geometry within an MRI environment can sustain induced eddy currents; therefore the component is split into open-C sections with inserts rather than a continuous carbon envelope. Surface temperature during thermoforming for this application is kept at the lower end 250°C to minimise fibre print-through on the patient-facing surface, and the produced part is post-cured at 80°C for 4 h to raise crystallinity and dimensional stability after machining. One process boundary is that the PA12 matrix should not be exposed to repeated autoclave sterilisation above 121°C because cyclic steam exposure above the glass-transition temperature can alter panel flatness; chemical disinfection with quaternary ammonium compounds is used instead.
Footwear shank production for high-end cycling shoes and ski touring boots uses the moisture-stable PA12 matrix not only for wet flex modulus retention but because the consolidated carbon fabric can be cut into narrow 8–15 mm shanks without edge fraying. Blanks are heated by a pair of quartz IR emitters to 235–245°C surface temperature; lower heating is chosen because the thin section cools rapidly and higher temperatures cause matrix blush on visible carbon surfaces. The shanks are formed in a conformal cold tool at 40–60°C to create a fast quench, and demoulded parts are tested for flexural fatigue under an internal cyclic bending protocol at 2 Hz with a 500 N peak load. In production, one failure mode is incomplete consolidation at the shank’s tapered tip if the blank is not held under 5 bar minimum cavity pressure for the first 15 s. Creases and wrinkles appear when the tool has sharp radii smaller than 3 mm. The part is then abraded on the bonding face with 240-grit silicon carbide paper before injection overmoulding of a PA12 bridge; the roughened surface raises the measured lap-shear strength of the moulded bond line above 4 MPa in internal testing following ISO 4587:2003 methodology adapted to rigid substrates. Because the shank operates in a wet-flex environment, conditioning at 23°C and 50% RH for 24 h is performed before final flexural modulus measurement; this distinguishes the PA12 grade from PA6-based carbon shanks that show larger modulus drop after moisture uptake. Published data for this exact carbon/PA12 shank geometry is limited; the fatigue acceptance limit is therefore set from coupon-level strain-life data rather than from a universal footwear standard.
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Envalior Tepex Dynalite 206-C200(x)/45% PA12-CF59, Dry is a fully consolidated, semi-finished thermoplastic composite sheet in which a continuous carbon-fiber fabric is embedded in a polyamide 12 matrix. The product designation decomposes into several process-relevant parameters: the 206 prefix identifies the fabric architecture, C200 denotes carbon reinforcement with nominal areal mass of 200 g/m², and the 45% suffix is the nominal fiber volume fraction after consolidation. The matrix field PA12-CF59 identifies a polyamide 12 formulation with a manufacturer-specific CF59 additive or filler package. The term Dry specifies moisture-controlled packaging and does not eliminate the need for a pre-drying step before molding. Published data for the CF59 matrix suffix is limited; therefore, processing boundaries should be verified against lot certificates and the manufacturer’s technical datasheet rather than generic PA12 literature.
The consolidated thickness of a single ply can be estimated from the fabric areal mass, carbon-fiber density, and fiber volume fraction. Taking a carbon-fiber density of 1.8 g/cm³ and a fiber volume fraction of 45%, the nominal ply thickness is calculated as t = 200 g/m² / (1.8 g/cm³ × 0.45) = 0.247 mm, approximately 0.25 mm per consolidated layer. The balanced fabric architecture gives similar in-plane stiffness and strength in the 0° and 90° directions when tested as a consolidated laminate. Tensile properties of fiber-reinforced thermoplastic composites are measured according to ISO 527-4:2021, while flexural properties are measured according to ISO 14125:1998. The density of the consolidated sheet is measured according to ISO 1183-1:2019 and typically falls in the range 1.40 g/cm³ to 1.45 g/cm³ depending on the CF59 matrix additive package. Void content is controlled by the manufacturer and is typically below 2% when cross-sections are evaluated by optical microscopy; however, acceptance limits are part-specific and should be taken from the production specification.
The carbon-fiber fabric contributes the majority of in-plane modulus. At 45% fiber volume fraction, the rule-of-mixtures longitudinal modulus of a unidirectional carbon/polyamide ply is approximately 0.45 × 230 GPa; however, woven fabric reduces effective stiffness because fiber undulation lowers in-plane modulus. Design data for this specific 206-C200(x) fabric should therefore be taken from measured coupons, not from unidirectional tape data. The exact crimp factor, drape limit, and nesting behavior of the fabric must be obtained from the manufacturer.
The PA12-CF59 matrix is a semi-crystalline aliphatic polyamide 12 formulation. Polyamide 12 has a lower amide-group density than polyamide 6 or polyamide 66, which reduces equilibrium moisture absorption and yields more stable dimensions under changing relative humidity. Under ISO 62:2008, a polyamide 12 matrix typically absorbs 0.7% to 1.0% moisture at 23 °C and 50% RH, while PA6 typically absorbs 2.5% to 3.0% under the same conditions. This difference becomes relevant where the part is exposed to humidity cycling because moisture uptake in the matrix alters matrix-dominated transverse modulus, creep, and failure strain. The glass transition temperature of dry polyamide 12 is usually in the range 45 °C to 55 °C, and its crystalline melting peak measured by differential scanning calorimetry per ISO 11357-3:2018 is typically 170 °C to 180 °C. The CF59 suffix does not change the polymer backbone but may alter melt viscosity, color, and thermal conductivity through filler addition. Melt-flow and thermal-conductivity values should be taken from the lot certificate rather than from generic PA12 literature.
Thermoforming and compression molding of the dry sheet require the stack to cross the PA12 crystalline melting range while remaining below the oxidative degradation threshold. The recommended melt-processing window for polyamide 12 composites is 220 °C to 250 °C. Below 220 °C the matrix viscosity is high enough to inhibit intra-laminate wet-out and interlaminar bonding of stacked plies; above 250 °C, prolonged residence can produce yellowing, chain scission, and reduction in toughness. The practical processing window is therefore narrow compared with polypropylene-based organosheets. In production infrared heating lines, edge overheating and core underheating are common failure routes when multilayer stacks exceed 6 to 8 plies because radiant energy is absorbed first at the surface. Convection ovens reduce thermal non-uniformity but increase cycle time. The stack should be rotated or heater zones trimmed if surface temperature differentials exceed 10 °C.
Infrared heating systems for PA12-CF59 are typically configured with ceramic or quartz emitters operating at wavelengths between 2.5 µm and 3.5 µm. Carbon-filled organosheets absorb strongly in the near-infrared; however, the surface temperature can rise rapidly while the core temperature lags. For a stack thickness of 2 mm, the difference between surface and core temperatures can exceed 20 °C if the heater intensity is set too high. Closed-loop pyrometers aimed at the surface and thermocouples placed in sacrificial edge tabs are used to map temperature uniformity. The heating cycle is typically divided into a soak phase at lower emitter power and a rapid ramp phase to final core temperature. If the sheet is heated too quickly from cold, thermal expansion of the outer plies can produce debonding at the ply interfaces before matrix melting occurs.
Pre-drying remains necessary even for Dry-grade material. Moisture exposure at relative humidity above 60% can increase surface moisture to levels that create porosity during heating. A heated-air dryer set at 80 °C for 4 h to 8 h is commonly used for PA12-based sheet; residual moisture should be verified below 0.1 wt% by ISO 15512:2019. Drying time should be extended for stacks that have been exposed to unconditioned air for more than 24 h. After drying, the sheet should be transferred to the heating station in a sealed pouch or under low-humidity conditions. At room temperature, PA12 absorbs moisture slowly, but the dry condition can be lost if packaging is opened in humid air. For critical molded parts, the dried sheet should not be left in an uncontrolled environment for more than 30 min before heating.
Compression molding tooling for PA12-CF59 is typically held at 80 °C to 120 °C to control crystallization and reduce warpage. Lower mold temperatures increase cooling rate and may produce under-crystallized matrix regions with reduced solvent resistance. Higher mold temperatures can extend cycle time and increase sticking if release films are inadequate. The holding pressure applied during consolidation is typically in the range 10 bar to 30 bar of cavity area, but this must be derived from part area, stack thickness, and tool rigidity. Void formation during consolidation is controlled by the balance between matrix melt pressure and trapped air or moisture. If mold closure is too slow, the matrix may solidify before the plies are fully debulked. If closure is too rapid, air trapped at the center cannot escape and forms porosity. Vacuum-assisted mold closure or staged pressure application is used in production tools to reduce void content. The effectiveness of consolidation can be checked by ultrasonic C-scan after molding; attenuation areas above the acceptance limit indicate interlaminar voids or delamination.
Because PA12 crystallizes more slowly than PA6 under rapid cooling, the compression mold may require a longer holding phase to allow sufficient crystallization before demolding. The cooling rate at the part surface is controlled by mold temperature and by the thermal resistance of the release film. If the part is demolded before the matrix reaches a sufficient degree of crystallinity, post-demolding crystallization can produce distortion. A tool-mounted temperature sensor or a pyrometric scan of the surface before demolding is used to verify that the part has fallen below 120 °C before ejection.
Hybrid parts are produced by thermoforming the organosheet and then injecting a PA12-based compound to form ribs, bosses, and edge stiffening. The insert surface must be heated above 170 °C at the moment the overmolding melt contacts it; otherwise the interface will cool below the crystallization temperature and create a weak boundary. This is normally achieved by keeping the insert in the mold at 80 °C to 120 °C and by using melt temperatures of 230 °C to 250 °C in the overmolding barrel. Screw recovery settings, injection speed, and packing pressure should be selected so that the PA12 melt does not degrade at the hot runner. Published processing data for the CF59 matrix is limited, and pilot trials are required to establish the maximum residence time in the barrel at 250 °C.
Tool surfaces in contact with the organosheet should be dimensioned to accommodate the 0.25 mm per ply thickness after compression. When multiple plies are used, thickness accumulation at overlaps and local fabric shifting can create thickness variation exceeding 5% of nominal, which must be addressed by tool gap adjustment or local pressure intensifiers. Failure to account for thickness variation can result in overmolding flash or incomplete filling at the interface. PA12 has lower mold shrinkage than PA6 or PA66. When overmolding PA12 compound onto PA12-CF59, shrinkage difference is lower than if a PA6 overmolding compound is used. The coefficient of linear thermal expansion of carbon-fiber PA12 in the plane is low, typically 2 × 10⁻⁶ K⁻¹ to 5 × 10⁻⁶ K⁻¹ in the fiber direction depending on fabric; through-thickness expansion is higher. This anisotropy must be considered when designing cooling channels and demolding sequences.
When PA12-CF59 is compared with PA6- and PA66-based Tepex Dynalite grades, the first measurable difference is moisture uptake. Under ISO 62:2008, PA12 absorbs less moisture at equilibrium than PA6 and PA66; this reduces thickness change and preserves matrix-dominated properties after humid exposure. The second difference is thermal: PA12 processes at 220 °C to 250 °C, whereas PA6 organosheets are typically processed at 250 °C to 270 °C and PA66 grades at 270 °C to 290 °C. Lower processing temperature reduces energy input but narrows the infrared heating window and may require longer mold residence time because crystallization is slower. A third difference is low-temperature toughness; PA12 retains higher impact ductility below -20 °C than PA6 or PA66 at equivalent moisture content.
| Matrix | Melting peak by ISO 11357-3:2018 | Typical processing range | Moisture at 23 °C/50% RH by ISO 62:2008 |
|---|---|---|---|
| PA12-CF59 | 170 °C to 180 °C | 220 °C to 250 °C | 0.7% to 1.0% |
| PA6 | 220 °C to 225 °C | 250 °C to 270 °C | 2.5% to 3.0% |
| PA66 | 260 °C to 265 °C | 270 °C to 290 °C | 2.0% to 2.5% |
The carbon fiber reinforcement dominates longitudinal tensile modulus and strength in all three matrix families; therefore, fiber-direction tensile modulus does not shift dramatically across PA12, PA6, and PA66 if areal weight and fiber volume fraction remain constant. Matrix-dominated properties such as transverse tensile strength, short-beam shear strength under ISO 14130:1997, and compression after impact are more sensitive to the matrix change and to moisture. Specific product comparisons should be performed on identical stacking sequences because thickness and fiber orientation weighting affect the result. Under cyclic loading, carbon-fabric PA12 laminates show fiber-dominated tension-tension fatigue behavior. Fatigue testing is conducted under ISO 13003:2003 or ASTM D3479/D3479M-19. The presence of the PA12 matrix with higher strain at break in dry and low-temperature conditions supports matrix cracking resistance; however, at elevated temperature above 80 °C, matrix-dominated fatigue life may decrease. Design allowables for dynamic parts should be generated from component-level testing because coupon data do not capture overmolded rib stresses and tooling-induced fiber distortion.
The CF59 matrix formulation may also influence surface appearance, laser marking contrast, or electrical surface resistivity. Where surface resistivity is a design requirement, measurement should follow IEC 62631-3-2 or ASTM D257-14, and acceptance values should be obtained from the lot certificate; published data for the CF59 suffix is limited. Environmental stress cracking of polyamide 12 can occur in the presence of certain plasticizers, organic salts, and strong solvents at elevated temperature. Parts exposed to fuel blends, biodiesel, or road salts should be tested under ISO 22088-3:2003 or ISO 16750-5. The CF59 matrix filler package may change surface wetting and chemical resistance; published data for this specific configuration is limited.
Application sectors for carbon-fabric PA12 organosheets include orthopedic braces and prosthetic sockets where low moisture uptake, fatigue resistance, and formability against tooling are required. Structural acceptance of prosthetic test coupons is often performed under ISO 10328:2006 or regional equivalents, although the specific laminate lay-up must be qualified separately. Sports equipment such as snowboard bindings, ski touring components, and carbon shoe inserts uses the material in thin, stiff shells that are subsequently overmolded with PA12 compounds for ribbing and attachment features. Automotive brackets and battery-compartment covers selected for hydrocarbon resistance and low-temperature impact can be converted from PA6-based organosheets to PA12-CF59 when humidity exposure is the limiting design condition. For any application involving sustained load above 80 °C, matrix creep should be evaluated by dynamic mechanical analysis or ISO 899-1:2017 creep testing, because the polyamide 12 matrix softens progressively above its glass transition.
The material should not be exposed to concentrated mineral acids, phenol, or molten salts; polyamide 12 is also attacked by strong oxidizing agents and may soften in boiling water over extended periods. In assemblies containing aluminum alloys, direct carbon-fiber-to-aluminum contact can create galvanic corrosion in the presence of an electrolyte; a non-conductive isolation layer or sealing is required at the interface. For parts exposed to automotive fluids, compatibility with long-life coolants and brake fluids should be validated under ISO 175:2010 or ISO 22088-3:2003 immersion protocols, because the PA12 matrix can plasticize at elevated temperature even if room-temperature uptake is low.
