US20200156355A1 - Multi-layer isotropic films having toughness, high temperature performance, and uv absorption - Google Patents

Multi-layer isotropic films having toughness, high temperature performance, and uv absorption Download PDF

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US20200156355A1
US20200156355A1 US16/630,132 US201816630132A US2020156355A1 US 20200156355 A1 US20200156355 A1 US 20200156355A1 US 201816630132 A US201816630132 A US 201816630132A US 2020156355 A1 US2020156355 A1 US 2020156355A1
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layer
mils
rpm
film
melt
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Inventor
Stephen A. Johnson
Derek W. Patzman
Richard Yufeng Liu
Victor Ho
Timothy J. Hebrink
Kevin T. Huseby
John F. VanDerlofske, III
John P. Purcell
William T. Fay
James B. Svacha
Richard J. Thompson
Timothy J. Lindquist
Kristopher J. Derks
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3M Innovative Properties Co
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3M Innovative Properties Co
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Abandoned legal-status Critical Current

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Definitions

  • UV ultraviolet
  • Isotropic low haze films are known. For example, acrylic and COC sheets/rolls are available in the marketplace. However, these films suffer from challenging physical properties, and thin versions of isotropic films such as these (or copolyesters) are extremely expensive, if available at all, and are very challenging to work with. Also, these films do not inherently provide for the required amount of UV light blockage.
  • a first multi-layer film includes, in the following order, an orienting layer, a peel layer, and an isotropic layer.
  • the orienting layer, the peel layer, and the isotropic layer all comprise an extrudable material and are oriented.
  • a second multi-layer film includes, in the following order, a first orienting layer, a first peel layer, an isotropic layer, a second peel layer, and a second orienting layer.
  • the first and second orienting layers, the first and second peel layers, and the isotropic layer all comprise an extrudable material and are oriented.
  • a third multi-layer film includes, in the following order, a first isotropic layer, a first peel layer, an orienting layer, a second peel layer, and a second isotropic layer.
  • the first and second isotropic layers, the first and second peel layers, and the orienting layer all comprise an extrudable material and are oriented.
  • a fourth multi-layer film includes, in the following order, a first isotropic layer, an orienting layer, a tie layer, a peel layer, and a second isotropic layer.
  • the first and second isotropic layers, the tie layer, and the peel layer all comprise an extrudable material and are oriented.
  • a fifth multi-layer film includes, in the following order, a first isotropic layer, a first peel layer, a first tie layer, an orienting layer, a second tie layer, a second peel layer, and a second isotropic layer.
  • the first and second isotropic layers, the first and second peel layers, the first and second tie layers, and the orienting layer all comprise an extrudable material and are oriented.
  • a sixth multi-layer film includes, in the following order, a first orienting layer, an isotropic layer, and a second orienting layer.
  • the first and second orienting layers and the isotropic layer all comprise an extrudable material and are oriented.
  • a seventh multi-layer film includes, in the following order, a first isotropic layer, an orienting layer, and a second isotropic layer.
  • the orienting layer and the first and second isotropic layers all comprise an extrudable material and are oriented.
  • An eighth multi-layer film includes, in the following order, a first orienting layer, a first isotropic layer, a tie layer, a second isotropic layer, and a second orienting layer.
  • the first and second orienting layers, the first and second isotropic layers, and the tie layer all comprise an extrudable material and are oriented.
  • a ninth multi-layer film includes, in the following order, a first orienting layer, a tie layer, and a second orienting layer.
  • the first and second orienting layers and the tie layer all comprise an extrudable material and are oriented.
  • multi-layer films include any of these nine or other embodiments with an extruded, but not oriented, carrier layer instead of an orienting layer and with the other layers not necessarily being extrudable nor oriented.
  • FIG. 1 is a side view of a three-layer film embodiment
  • FIG. 2 is a side view of a four-layer film embodiment
  • FIG. 3 is a side view of a five-layer film embodiment
  • FIG. 4 is a side view of a five-layer film embodiment
  • FIG. 5 is a side view of a five-layer film embodiment
  • FIG. 6 is a side view of a seven-layer film embodiment
  • FIG. 7 is a side view of a three-layer film embodiment
  • FIG. 8 is a side view of a three-layer film embodiment
  • FIG. 9 is a side view of a five-layer film embodiment.
  • FIG. 10 is a side view of a three-layer film embodiment.
  • Embodiments of this invention include multi-layer films, and processes to make the films, that enable the delivery of a substrate featuring a peelable thin layer of low haze, amorphous, isotropic film with the desired properties of high modulus, high usage temperature, UV blockage, and toughness.
  • a multi-layer co-extrusion, co-orientation and annealing process is used to enable the delivery of a thin isotropic, UV blocking layer on top of a release layer and support substrate.
  • These film constructions can be kept together during additional processing steps such as coating and converting.
  • the release and dimensionally stable substrate layer can be easily removed once processing steps are completed.
  • Solvent coating the exemplary isotropic materials for the multi-layer films of this invention would be challenging, as solubility of higher MW (20,000+ amu) aromatic polyesters is very limited. Low solids, and undesirable solvent choices such as trifluoroacetic acid or o-cholorbenzene/phenol are two examples of the limited set of solvents which can provide some level of solubility.
  • Extrusion coating wide clean, uniform layers of material can also be quite challenging. Thin extrusion coated layers are frequently limited by melt integrity, line speed capability and caliper control, and tend to have a lower bound of around 20 microns. Additionally, the co-extrusion process itself imparts a degree of birefringence/retardance to many polymers, including the materials used in the multi-layer films of this invention.
  • Thin, low haze films that exhibit surprisingly low isotropic performance have been made through a process which involves co-extrusion with a carrier substrate providing dimensional stability and a peel layer, co-orientation of the layers of film and annealing the film.
  • the orientation and annealing process for the multi-layer films of the present invention reduces the birefringence/retardance to desirable levels.
  • the co-extrusion process for the multi-layer films of the present invention can provide pristine clean surfaces and avoids the surface defects and die build-up (oligomer) issues typical to the extrusion coating process.
  • FIG. 1 is a side view of a three-layer film 10 having an ABC layer configuration.
  • Film 10 includes the following layers in the configuration as shown: an orienting Layer A ( 12 ); a peel Layer B ( 14 ); and an isotropic Layer C ( 16 ).
  • This configuration of film 10 provides for an isotropic layer (Layer C) with the stabilizing Layer A and the peel Layer B.
  • FIG. 2 is a side view of a four-layer film 18 having an ADBC layer configuration.
  • Film 18 includes the following layers in the configuration as shown: an orienting Layer A ( 20 ); a tie Layer D ( 22 ); a peel Layer B ( 24 ); and an isotropic Layer C ( 26 ).
  • This configuration of film 18 provides the additional capability of controlling where the first separation of layers will occur, in this case between the Layers B and C.
  • FIG. 3 is a side view of a five-layer film 28 having an ABCBA layer configuration.
  • Film 28 includes the following layers in the configuration as shown: an orienting Layer A ( 30 ); a peel Layer B ( 32 ); an isotropic Layer C ( 34 ); a peel Layer B ( 36 ); and an orienting Layer A ( 38 ).
  • This configuration of film 28 enables pristine, sterile surfaces of the isotropic layer (Layer C).
  • FIG. 4 is a side view of a five-layer film 40 having a CBABC layer configuration.
  • Film 40 includes the following layers in the configuration as shown: an isotropic Layer C ( 42 ); a peel Layer B ( 44 ); an orienting Layer A ( 46 ); a peel Layer B ( 48 ); and an isotropic Layer C ( 50 ).
  • This configuration of film 40 enables dual production of the isotropic layers (Layer C).
  • FIG. 5 is a side view of a five-layer film 52 having a CADBC layer configuration.
  • Film 52 includes the following layers in the configuration as shown: an isotropic Layer C ( 54 ); an orienting Layer A ( 56 ); a tie Layer D ( 58 ); a peel Layer B ( 60 ); and an isotropic Layer C ( 62 ).
  • This configuration of film 52 enables controlled release of the isotropic layer (Layer C) and also enables superior curl control of the film.
  • FIG. 6 is a side view of a seven-layer film 64 having a CBDADBC layer configuration.
  • Film 64 includes the following layers in the configuration as shown: an isotropic Layer C ( 66 ); a peel Layer B ( 68 ); a tie Layer D ( 70 ); an orienting Layer A ( 72 ); a tie Layer D ( 74 ); a peel Layer B ( 76 ); and an isotropic Layer C ( 78 ).
  • This configuration of film 64 combines controlled release and dual production of the isotropic layers (Layer C).
  • FIG. 7 is a side view of a three-layer film 80 having an ACA layer configuration.
  • Film 80 includes the following layers in the configuration as shown: an orienting Layer A ( 82 ); an isotropic Layer C ( 84 ); and an orienting Layer A ( 86 ).
  • This configuration of film 80 provides for an isotropic layer (Layer C) with the stabilizing layers (Layers A).
  • FIG. 8 is a side view of a three-layer film 88 having a CAC layer configuration.
  • Film 88 includes the following layers in the configuration as shown: an isotropic Layer C ( 90 ); an orienting Layer A ( 92 ); and an isotropic Layer C ( 94 ). This configuration of film 88 enables dual production of the isotropic layers (Layers C).
  • FIG. 9 is a side view of a five-layer film 96 having an ACDCA layer configuration.
  • Film 96 includes the following layers in the configuration as shown: an orienting Layer A ( 98 ); an isotropic Layer C ( 100 ); a tie Layer D ( 102 ); an isotropic Layer C ( 104 ); and an orienting Layer A ( 106 ).
  • This configuration of film 96 enables additional functionality of the isotropic layers (Layers C) by incorporating a polymer material (Layer D) between the isotropic layers.
  • FIG. 10 is a side view of a three-layer film 108 having an ADA layer configuration.
  • Film 108 includes the following layers in the configuration as shown: an orienting Layer A ( 110 ); a tie Layer D ( 112 ); and an orienting Layer A ( 114 ).
  • This configuration of film 108 enables a single layer of thermoplastic material (Layer D) with the stabilizing layers (Layers A).
  • the multi-layer film constructions of FIGS. 1-10 can be made by co-extrusion of the materials for the layers, followed by orientation and annealing of the co-extruded layer materials.
  • Materials sets utilized in making these multi-layer films include the following.
  • the Layer A materials are preferably PEN or Low Melt PEN which are available from 3M Company.
  • PEN can be described as a 0.48 IV polyethylene naphthalate polymer.
  • Low Melt PEN can be described as a 0.48 IV copolyester comprised of 90 mol % naphthalate moieties and 10 mol % terephthalate moieties on an esters basis.
  • Ethylene glycol comprises the diols in this polymer.
  • the Layer A is an orienting layer that serves as the carrier vehicle, support substrate, enabling flat film production during both the orientation and annealing process. Post-annealing, the Layer A serves to provide high modulus and dimensional stability.
  • the Layer B materials are preferably a blend of the following materials: a polypropylene or co-polypropylene capable of co-extrusion and co-orientation with the A, C and D Layers.
  • a polypropylene or co-polypropylene capable of co-extrusion and co-orientation with the A, C and D Layers.
  • An example of these materials is Pro-Fax SR549M, a co-polypropylene (7% polyethylene) available from Lyondell-Basell.
  • These polypropylenes comprise 70 or more wt % of the Layer B and are a blend with one or more of the following: an SEBS/SEPS block copolymer capable of co-extrusion and co-orientation with the Layers A, C and D.
  • these materials include Kraton G1645 and Kraton G1657 available from the Kraton Corporation.
  • the Layer B may also contain an olefinic antistat agent capable of co-extrusion and co-orientation with the Layers A, C, and D, which will enhance electrostatic pinning in the film casting process.
  • An exemplary antistat resin is Pelestat 230 available from Sanyo Chemical Industries.
  • the Layer B is a peel layer designed to provide approximately 5 to 40 gli of adhesion to the Layers A or C.
  • the Layer C materials are preferably a coPEN polymer known as PENg.
  • PENg30 is a coPEN polyester available from 3M Company.
  • the manufacturing method and material composition (100% NDC on esters, 70 mol % ethylene glycol and 30 mol % CHDM on a diols basis) is more completely described in the Examples.
  • PENg50 are also coPEN polyesters with 40 mol % and 50 mol % CHDM on a diols basis and are also more completely described in the Examples.
  • the Layer C is an isotropic layer that provides the functionality of, for example, a peelable thin layer of low haze, amorphous, isotropic film with desired properties of high modulus, high usage temperature, UV blockage, and toughness.
  • the optional Layer D material or materials are most preferably an elastic olefin or olefin blend exhibiting excellent adhesion (>300 gli) to polyesters. These olefins must be capable of co-extrusion and co-orientation with the Layers A, B, and C. Exemplary elastic olefins include Kraton G1645 and Kraton G1657 available from the Kraton Corporation. These materials can also be blended with low levels of other materials such as SR549M or Pelestat 230 to tailor physical and adhesion properties and/or to enhance electrostatic pinning performance.
  • the Layer D functions as a tie layer.
  • a carrier layer can be used instead of an orienting layer.
  • the carrier layer can be extruded but not oriented.
  • An example of a carrier layer is polyethylene film.
  • the other layers of the film need not be extrudable nor oriented, and the film can be made using a blown film process, for example.
  • polyester copolymers were produced using the following procedure:
  • NDC Dimethyl-2,6-Naphthalene Dicarboxylate
  • CHDM Cyclohexanedimethanol
  • Tetrabutyl Titanate obtained from Dorf Ketal, Houston, Tex.
  • CoAc Cobalt Acetate
  • Zinc Acetate obtained from Mallinckrodt Baker, Phillipsburg, N.J.
  • Antimony Triacetate (SbAc)—obtained from Arkema, Philadelphia, Pa.
  • a portion from each exemplary resin was then placed in a 150 C oven for 48 hours to induce cold crystallization.
  • the cold-crystallized materials were then tested using Differential Scanning Calorimetry, or DSC (Q2000 commercially available from TA Instruments, New Castle, Del.).
  • the test involved a 3-stage heating-cooling-heating temperature regimen over a temperature range from 30 C to 290 C.
  • the test specimen was held at 290 C for 3 min after the first heat.
  • the temperature-ramp rate was 20 C/min for both heating and cooling. Both the first heating scan and the second heating scan were recorded and analyzed.
  • Table 2 captures the findings for melt point and associated melting enthalpy (delta H).
  • Tg glass transition temperature
  • Table 2 shows that Examples 1, 2 and 3, (PENg30, PENg40 and PENg50, respectively), exhibit melt points of 210 C or lower with little to no melting enthalpy ( ⁇ 3 J/g).
  • the Tg of all six materials in this table were measured to be between 115 C and 120 C.
  • a series of 3-component 5-layer films in an A/B/C/B/A layer configuration were produced via co-extrusion, stretching, and annealing. These five layer films used a layer configuration consistent with FIG. 3 .
  • the A Layer resin was a PEN homopolymer of 0.48 IV, prepared in-house.
  • the feed rate of the PEN was 4.54 kg/hr.
  • the B Layer resin was a 9:1 blend (by weight) of Pro-Fax SR549M, an 11 MFI (melt flow index) clarified polypropylene random copolymer obtained from Lyondell-Basell, Houston Tex., and Kraton 1645, a 3 MFI Styrene-Ethylene/Butadiene-Styrene (SEBS) triblock copolymer obtained from Kraton Corporation, Houston Tex.
  • the feed rate of this blend was 2.27 kg/hr
  • the C Layer resin varied among these Examples and Comparative Example.
  • Ex. 4 used the resin of Ex. 1, PENg30, as C Layer resin.
  • Ex. 5 used the resin of Ex. 2, PENg40, as C Layer resin.
  • Ex. 6 used the resin of Ex. 3, PENg50, as C Layer resin.
  • Comp. Ex. C4 used the resin of Ex. C3, PENg60, as C Layer resin.
  • the feed rate of the C Layer resin was 4.54 kg/hr
  • the outer, or A, Layers were produced by extruding PEN resin with a 27 mm twin screw extruder (TSE) through a gear pump and neck tube into the outer layers of a 5-layer feed block.
  • TSE twin screw extruder
  • This melt train used a progressive temperature extrusion profile, with peak temperature of about 285 C.
  • the intermediate, or B, Layers were produced by feeding both of the above-identified resins to a 27 mm TSE having a progressive temperature profile peaking at about 260 C, then to and through a gear pump and neck tube, and into the 2 nd and 4 th layers of the 5-layer feed block.
  • the core, or C, Layer was produced by extruding the above-identified resin through a 25 mm TSE with a gear pump and neck tube, feeding into the 3 rd , or center, layer of the 5-layer feed block.
  • a progressive temperature profile was used, with peak temperature of about 285 C.
  • the feed block fed an 8′′ (20.3 cm) film die, and these were held at a temperature of about 285 C.
  • the molten extrudate was cast to a casting wheel maintained at a temperature of about 50 C. Cast webs of about 36 mil (0.91 mm) thickness were produced during this process.
  • the cast webs produced from the extrusion and casting process were then stretched and annealed using a KARO IV lab stretcher obtained from Brueckner Maschinenbau, Siegsdorf, Germany. Stretching of the film took place in an oven at a temperature of about 140 C. Preheating duration was about 45 seconds. Films were stretched simultaneously biaxially to a final dimension of 350% by 350% of the original size, resulting in a finished film of about 3 mils (75 microns). These films were then conveyed into an annealing oven maintained at about 225 C and held at that temperature for 15 seconds. These stretched, annealed films were then evaluated for refractive index, haze, and transmission. The unstretched cast webs were also evaluated for refractive index.
  • the refractive indices of specimens of these Examples were measured using a Metricon Prism coupler (Metricon Corporation, Pennington, N.J.) in the machine direction (MD), transverse direction (TD) and thickness (TM) directions.
  • the refractive indices of MD, TD and TM are labeled Nx, Ny and Nz respectively.
  • Average in-plane index represents the average of the Nx and Ny refractive index measurements for a given sample.
  • Out-of-plane Birefringence represents the difference between the average in-plane index and the index normal to the film (Nz).
  • % Haze was measured using a Haze-Gard instrument from BYK-Gardner USA, Columbia, Md. Haze was measured according to ASTM D-1003.
  • % T 370 nm refers to % transmission of the isotropic cast web at 370 nm which was measured using a Shimadzu UV/Vis spectrometer (Shimadzu Scientific Instruments, Columbia, Md.).
  • Table 3 shows that cast webs for Examples 4, 5, 6 and Comparative Example C4 all exhibit low out-of-plane birefringence ( ⁇ 0.01). However, only Examples 4, 5 and 6 maintain a low level of out-of-plane birefringence ( ⁇ 0.01) after stretching and annealing. All Examples exhibited low % Haze. All Examples also exhibit high levels of UV blockage at 370 nm, with % T levels ⁇ 10% for examples 4, 5, and 6.
  • Low Melt PEN refers to a 0.48 IV (g/dL) copolyester comprising 90 mol % naphthalate moieties and 10 mol % terephthalate moieties on an esters basis.
  • the diol component is 100% ethylene glycol.
  • Low Melt PEN was synthesized in-house.
  • Pelestat 230 refers to a polyether-polyolefin antistatic block copolymer available from Sanyo Chemical Industries, Kyoto, Japan.
  • the outer, or C, Layers were produced by extruding PENg30 (as described in Example 1) resin with a 27 mm twin screw extruder (TSE) through a gear pump and neck tube into the outer layers of a 5-layer feed block.
  • TSE twin screw extruder
  • This melt train used a progressive temperature extrusion profile, with peak temperature of about 270 C.
  • One intermediate layer, the B Layer was produced by feeding both of the above-identified resins to an 18 mm TSE having a progressive temperature profile peaking at about 260 C, then to and through a gear pump and neck tube, and into the 4 th layer of the 5-layer feed block.
  • Another intermediate layer, the A Layer was produced by feeding the above-identified resin to an 27 mm TSE having a progressive temperature profile peaking at about 285C, then to and through a gear pump and neck tube, and into the 2 nd layer of the 5-layer feed block.
  • the center, or D, Layer was produced by extruding the above-identified resin through a 25 mm TSE with a gear pump and neck tube, feeding into the 3 rd , or center, layer of the 5-layer feed block.
  • a progressive temperature profile was used, with peak temperature of about 260 C.
  • the feed block fed an 8′′ (20.3 cm) film die, and these were held at a temperature of about 285 C.
  • the molten extrudate was cast to a casting wheel maintained at a temperature of about 50 C. Cast webs of about 24 mil (0.61 mm) thickness were produced during this process.
  • the cast webs produced from the extrusion and casting process were then stretched and annealed using a KARO IV lab stretcher obtained from Brueckner Maschinenbau, Siegsdorf, Germany. Stretching of the film took place in an oven at a temperature of about 140 C. Preheating duration was about 30 seconds. Films were stretched simultaneously biaxially to a final dimension of 350% by 350% of the original size, resulting in a finished film of about 2 mils (50 microns). These films were then conveyed into an annealing oven maintained at about 225 C and held at that temperature for 15 seconds. These stretched, annealed films were then evaluated for refractive index, haze, and peel force. The unstretched cast webs were also evaluated for refractive index.
  • Peel force of films was evaluated using an Imass SP-2100 (Imass, Inc., Marshfield, Mass.) using a standard 90 degree peel test. It should be noted that for all three Examples, the peel layer (B) and the isotropic layer (C) exhibit peel forces of less than 10 Win (3.9 g/cm), while the tie layer (D) and the orienting layer (A) exhibit peel forces of greater than 500 Win (200 g/cm). The peeled isotropic layer in these Examples exhibits low haze and low out-of-plane birefringence.
  • Example 4 exhibit excellent solvent resistance to cyclohexanone, n-butyl acetate and propyl glycol methyl ether acetate when exposed to each of these solvents for 5 minutes at room temperature. No evidence of swelling, cracking, or distorting was apparent.
  • a series of multi-layer films were produced via co-extrusion blown film process.
  • the materials inputs for the examples of the ACA ( FIG. 7 ) and ABCBA ( FIG. 3 ) film layer stacks are provided in Table 6.
  • the skin layers (A) were produced by extruding DOW611A polyethylene resin through 20 mm single screw extruders with about a 30:1 length to diameter ratio and adapters into layers 1, 2, 3, 6, and 7 of a seven-layer annular stack die (obtained under the trade designation “COEX 7-LAYER” (Type LF-400) from Labtech Engineering, Samutprakarn, Thailand). These melt trains used a progressive temperature extrusion profile, with peak temperatures of ⁇ 210 C.
  • the core layers (C) were produced by extruding the above-identified resins through an 20 mm single screw extruders with about a 30:1 length to diameter ratio and adapters into the 4 th and 5 th layers of the seven-layer annular stack die.
  • melt trains used a progressive temperature extrusion profile, with peak temperatures around 255C.
  • the pancake die and mandrel were held at a target temperature of 227 C.
  • the blower motor output was held around 3000 rpm.
  • the bubble was subsequently collapsed about ten feet above the die and rolled up.
  • the films produced were measured for transmission, haze, and refractive index, as listed in Table 7.
  • the PENg30/40 sample target thicknesses were targeting a 1.5 mil film.
  • the outer layers (A) were produced by extruding DOW611A polyethylene resin through 2.5 inch single screw extruders through adapters into layers 1, 2, 3, 4, 6, 7, 8, and 9 of a nine-layer pancake blown film die. These melt trains used a progressive temperature extrusion profile, with peak temperatures of ⁇ 200 C.
  • the core layer (C) was produced by extruding the above-identified resin through a 2 inch single screw extruder with an adapter and dump valve into the 5 th layer of the nine-layer pancake blown film die. This melt train used a progressive temperature extrusion profile, with a peak temperature around 255 C. The pancake die and mandrel were held at a target temperature of 220 C.
  • the transmission, haze, and refractive index for these samples are listed in Table 9. These samples range in thickness from 0.25 mil to 2 mil. All the film samples were made from PENg30 except for sample 17-0825-3. This sample was made from PENg40. This explains the difference in refractive index.
  • haze is below 1% and transmission is higher than 90%, which are the targets for optically clear film.
  • the refractive index of the film does change based on the angle the index is measured. This is attributed to the forming ratio. As the forming ratio gets closer to 1, the film exhibits more balanced orientation.
  • the skin layers (A) were produced by extruding DOW611A polyethylene resin through 20 mm single screw extruders with about a 30:1 length to diameter ratio and adapters into layers 1, 2, 6, and 7 of a seven-layer annular stack die (obtained under the trade designation “COEX 7-LAYER” (Type LF-400) from Labtech Engineering, Samutprakarn, Thailand). These melt trains used a progressive temperature extrusion profile, with peak temperatures of ⁇ 210 C.
  • the core layers (C) were produced by extruding the above-identified resins through an 20 mm single screw extruders with about a 30:1 length to diameter ratio and adapters into the 3 rd , 4 th and 5 th layers of the seven-layer annular stack die. These melt trains used a progressive temperature extrusion profile, with peak temperatures around 265 C.
  • the annular stack die and mandrel were held at a target temperature of 265 C.
  • the blower motor output was held around 1800 rpm.

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