Classifications

• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
  • C08J5/18—Manufacture of films or sheets
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C67/00—Shaping techniques not covered by groups B29C39/00 - B29C65/00, B29C70/00 or B29C73/00
  • B29C67/24—Shaping techniques not covered by groups B29C39/00 - B29C65/00, B29C70/00 or B29C73/00 characterised by the choice of material
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
  • C08K5/00—Use of organic ingredients
  • C08K5/0008—Organic ingredients according to more than one of the "one dot" groups of C08K5/01 - C08K5/59
  • C08K5/0016—Plasticisers
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C71/00—After-treatment of articles without altering their shape; Apparatus therefor
  • B29C71/02—Thermal after-treatment
  • B29C2071/022—Annealing
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C48/00—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor
  • B29C48/001—Combinations of extrusion moulding with other shaping operations
  • B29C48/0018—Combinations of extrusion moulding with other shaping operations combined with shaping by orienting, stretching or shrinking, e.g. film blowing
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C48/00—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor
  • B29C48/022—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor characterised by the choice of material
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C48/00—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor
  • B29C48/03—Extrusion moulding, i.e. expressing the moulding material through a die or nozzle which imparts the desired form; Apparatus therefor characterised by the shape of the extruded material at extrusion
  • B29C48/07—Flat, e.g. panels
  • B29C48/08—Flat, e.g. panels flexible, e.g. films
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C71/00—After-treatment of articles without altering their shape; Apparatus therefor
  • B29C71/0063—After-treatment of articles without altering their shape; Apparatus therefor for changing crystallisation
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
  • B29K2067/00—Use of polyesters or derivatives thereof, as moulding material
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29L—INDEXING SCHEME ASSOCIATED WITH SUBCLASS B29C, RELATING TO PARTICULAR ARTICLES
  • B29L2007/00—Flat articles, e.g. films or sheets
  • B29L2007/008—Wide strips, e.g. films, webs
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J2367/00—Characterised by the use of polyesters obtained by reactions forming a carboxylic ester link in the main chain; Derivatives of such polymers
  • C08J2367/02—Polyesters derived from dicarboxylic acids and dihydroxy compounds
• • G—PHYSICS
  • G05—CONTROLLING; REGULATING
  • G05B—CONTROL OR REGULATING SYSTEMS IN GENERAL; FUNCTIONAL ELEMENTS OF SUCH SYSTEMS; MONITORING OR TESTING ARRANGEMENTS FOR SUCH SYSTEMS OR ELEMENTS
  • G05B2219/00—Program-control systems
  • G05B2219/30—Nc systems
  • G05B2219/49—Nc machine tool, till multiple
  • G05B2219/49029—Virtual rapid prototyping, create a virtual prototype, simulate rapid prototyping process

Definitions

• This invention relates to the preparation of flexible films or sheets from plasticized polyester compositions. More particularly, this invention relates to the preparation of such films or sheets that undergo induced crystallization, such as via calendering.
• polymeric materials such as poly(viny) chloride) (PVC) and cellulose esters such as cellulose acetate, cellulose acetate propionate and cellulose acetate butyrate must be plasticized to be processed into molded or extruded objects.
• PVC poly(viny) chloride)
• cellulose esters such as cellulose acetate, cellulose acetate propionate and cellulose acetate butyrate
• Most other thermoplastic resins such as polyesters, polyamides and polyolefins do not typically contain a plasticizer when processed in the molten state to form rigid molded or extruded objects.
• plasticizers in polyester compositions has been disclosed for various applications.
• U.S. Patent No. 4,450,250 to McConnell et al. describes adhesive compositions based on amorphous or crystallizable polyesters having a melting point in the range of 80 to 230°C containing 1 to 35 weight percent of selected plasticizers.
• U.S. Patent No. 4,340,526 to Petke et al. describes hot melt adhesive compositions based on certain terephthalate and 1 ,4- cyclohexanedicarboxylate polyesters containing 10 to 35 weight percent of benzoate or phthalate plasticizers.
• the plasticizers are present to lower the melt viscosity of the polyesters in order to facilitate their use as hot melt adhesives.
• Japan Patent No. 02 986197 to Kiyomi et al. describes extruded flat or tubular film based on polyesters plasticized with 1 to 40 parts of several types of plasticizer per 100 parts of polyester, i.e. up to 28 weight percent plasticizer in overall composition. Many of the plasticizers cited are of an aliphatic nature. The films are used as shrink films.
• polyester compositions comprising a blend of poly(1 ,4-cyclohexylenedimethylene terephthalate) (PCT) copolyesters containing at least 80 mole percent of
• U.S. Patent No. 5,824,398 to Shih describes heat shrinkable film or sheet comprising 90 to 99 weight percent of a polyester having a Tg in the range of 40 to 150°C and comprising at least 80 mole percent of aromatic dicarboxylic acids having 8 to 14 carbon atoms and at least 10 mole percent CHDM and 1 to 10 weight percent of a monoglyceride having 5 to 35 carbon atoms. The monoglyceride lowers the Tg of the blend.
• PET polyethylene terephthalate
• Additives include certain plasticizers, fast crystallizing polyesters such as poly(butylene terephthalate) (PBT), glass fibers and talc, which would act as a nucleation agent in PET.
• PBT poly(butylene terephthalate)
• polyester compositions having improved gas barrier properties for use in making film or sheet contain 80 to 99 weight percent of a homo or copolyester containing an aromatic dicarboxylic acid such as terephthalic acid and one or more glycols containing 2 to 12 carbon atoms and 1 to 20 weight percent of benzoic acid esters or phthalic acid esters.
• a homo or copolyester containing an aromatic dicarboxylic acid such as terephthalic acid
• glycols containing 2 to 12 carbon atoms and 1 to 20 weight percent of benzoic acid esters or phthalic acid esters.
• Great Britain Patent No. 815,991 to Goodale et al. describes a process for making dibenzoate esters from glycols and butyl benzoate using a calcium oxide ester exchange catalyst. These esters are reported to be plasticizers for PVC resins.
• thermoplastic polymers such as thermoplastic rubbers, certain polyurethanes, talc-filled polypropylene, acrylonitrile/butadiene/styrene terpolymers (ABS resins) and chlorinated polyethylene are sometimes processed by calendering methods.
• ABS resins acrylonitrile/butadiene/styrene terpolymers
• a process for preparing a film or sheet having a glass transition temperature below about 23°C and a melting temperature greater than about 120°C comprises the steps of: (a) preparing a polyester composition comprising
• a film or sheet has a glass transition temperature below about 23°C and a melting temperature greater than about 120°C and comprises a polyester composition comprising
• Figure 1 is a dynamic mechanical analysis, DMTA, curve of Examples 1 to 4.
• Figure 2 is a DMTA curve of Examples 5 to 8.
• Figure 3 is a DMTA curve of Examples 9 to 12.
• DETAILED DESCRIPTION OF THE INVENTION This invention relates to a process for preparing a film or sheet from a plasticized polyester composition.
• the film or sheet formed is soft and flexible having a glass transition temperature (Tg) below about 23°C, preferably below about 0°C, and a crystalline melting point (Tm) above about 120°C, preferably above about 140°C.
• Tg glass transition temperature
• Tm crystalline melting point
• the plasticized polyester composition undergoes induced crystallization either during or after the formation of the film or sheet.
• the process for preparing the film or sheet of the present invention comprises the steps of:
• the polyester composition comprises about 50 to about 95 weight percent, preferably about 50 to about 80 weight percent and more preferably about 60 to about 75 weight percent, of the base copolyester and about 5 to about 50 weight percent, preferably about 20 to about 50 weight percent and more preferably about 25 to about 40 weight percent, of the plasticizer or combination of plasticizers suitable for use with the base copolyester.
• the base copolyester has a melting temperature of less than about 220°C and exhibits more than about 1 percent crystallinity after annealing for 2000 minutes at a temperature of which the base copolyester has a maximum crystallization rate.
• the base copolyester of the polyester composition preferably comprises (i) a diacid component comprising residues of at least about 80 mole percent of a primary diacid selected from terephthalic acid, naphthalenedicarboxylic acid, 1 ,4-cyclohexanedicarboxylic acid, isophthalic acid or mixtures thereof and (ii) a diol component comprising residues of at least about 80 mole percent of at least one primary diol containing 2 to about 10 carbon atoms.
• the diacid component is based on 100 mole percent and the diol component is based on 100 mole percent.
• any of the various isomers of naphthalenedicarboxylic acid or mixtures of isomers may be used but the 1 ,4-, 1 ,5-, 2,6- and 2,7- isomers are preferred.
• cis, trans or cis/trans isomer mixtures of 1 ,4- cyclohexanedicarboxylic acid may be used.
• the diacid component may be modified with up to about 20 mole percent of a modifying diacid containing from about 4 to about 40 carbon atoms, such as succinic acid, glutaric acid, adipic acid, suberic acid, sebacic acid, azelaic acid, dimer acid, sulfoisophthalic acid or mixtures thereof.
• the preferred primary diol includes ethylene glycol, diethylene glycol, neopentyl glycol, 1 ,4-cyclohexanedimethanol or mixtures thereof. More preferably, the primary diol comprises residues of from about 10 to 100 mole percent 1 ,4- cyclohexanedimethanol (CHDM) and from about 90 to 0 mole percent ethylene glycol. Even, more preferably, the primary diol comprises residues of from about 10 to about 40 mole percent CHDM and from about 90 to about 60 mole percent ethylene glycol. The diol residue component may also be modified with up to about 20 mole percent of other diols.
• CHDM 1 ,4- cyclohexanedimethanol
• the diol residue component may also be modified with up to about 20 mole percent of other diols.
• Suitable modifying diols include 1 ,3-propanediol, propylene glycol, 1 ,4-butanediol, 1 ,5-pentanediol, 1 ,6-hexanediol, 1 ,8-octanediol, 2,2,4-trimethyl-1 ,3- pentanediol, 2,2,4,4-tetramethyl-1 ,3-cyclobutanediol, 1 ,3-CHDM or mixtures thereof. Also small amounts of polyalkylene glycols such as polyethylene glycol, polypropylene glycol, and polytetramethylene glycol may be used if desired.
• the CHDM moiety may be as the cis, trans or cis/trans mixture of isomers.
• melt viscosity and melt strength of the base copolyester are insufficient for suitable processing on calendering equipment.
• the use of a melt strength enhancer is desirable such as by the addition of small amounts (about 0.1 to about 2.0 mole percent) of a branching agent to the copolyester either during their initial preparation or during subsequent blending or feeding procedures prior to reaching the calendering equipment.
• Suitable branching agents include multifunctional acids or alcohols such as trimellitic acid, trimellitic anhydride, pyromellitic dianhydride, trimethylolpropane, glycerol, pentaerythritol, citric acid, tartaric acid, and 3-hydroxyglutaric acid.
• branching agents may be added directly to the copolyester or blended with the copolyester in the form of a concentrate as described in U.S. Pat. Nos. 5,654,347 and 5,696,176. It is also possible to use agents such as sulfoisophthalic acid to increase the melt strength of the polyester to a desirable level as disclosed in U.S. Pat. No. 5,399,595.
• copolyesters used in the present invention are readily prepared by melt phase techniques well known in the art. In addition, some of the copolyesters may be made by a combination of melt phase and solid phase polycondensation procedures also well known in the art.
• the inherent viscosity, IV, of useful polyesters will generally range from about 0.4 to about 1.5 dUg and preferably about 0.6 to about 1.2 dL/g. IV measurements are generally made at 25°C using 0.50 gram of polymer in 100 mL of a solvent composed of 60 weight percent phenol and 40 weight percent 1 ,1,2,2-tetrachloroethane.
• the plasticizer for use in the present invention should be suitable for use with the copolyester.
• the presence of the plasticizer is quite beneficial to lower the processing temperature of the polyester, to prevent sticking to the rolls, to eliminate predrying of the polyester and to create elastomeric materials having good mechanical properties.
• the preferred range of plasticizer content will depend on the properties of the base polyester and the plasticizer. In particular, the lower the Tg of the base copolyester and/or the plasticizer as predicted by the well-known Fox equation (T.G. Fox, Bull. Am. Phys. Soc, 1, 123 (1956)), the lesser the amount of plasticizer needed to obtain the polyester composition that produces a film or sheet having a Tg below 23°C.
• the preferred range of plasticizer content is from about 20 to about 50 weight percent and more preferably from about 25 to about 40 weight percent.
• Preferred plasticizers dissolve a film of the polyester to produce a clear solution at temperatures below about 160°C. This property of the plasticizer is referred to as its solubility.
• the procedure for determining whether a plasticizer has the appropriate solubility is as follows. Materials required for the test include a standard reference film of 5 mils (.127 mm) in thickness, a small vial, a heating block or oven and a plasticizer. The following steps are performed:
• step 4 for each of the following temperatures (°C): 75, 100, 140, 150, and 160.
• Plasticizer is a solid at this temperature
• the plasticizers that are most effective at solubilizing the polyester have a solubility of greater than 4 according to Table 1 and can also be classified according to their solubility parameter.
• the solubility parameter, or square root of the cohesive energy density, of a plasticizer can be calculated by the method described by Coleman et al., Polymer 31 , 1187 (1990), herein incorporated by reference.
• the most preferred plasticizers will have a solubility parameter ( ⁇ ) in the range from about 9.5 to about 13.0 cal 0-5 cm "1-5 .
• Table 2 demonstrates that plasticizers with a solubility parameter within this range solubilize the polyester while those plasticizers with a solubility parameter outside of this range are much less effective. In general, higher molecular weight plasticizers are preferred to prevent smoking and loss of plasticizer during the calendering process.
• plasticizers suitable for use in the present invention include esters based on an acid moiety selected from phthalic acid, adipic acid, trimellitic acid, benzoic acid, azelaic acid, terephthalic acid, isophthalic acid, butyric acid, glutaric acid, citric acid and phosphoric acid.
• the alcohol moiety is selected from aliphatic, cycloaliphatic or aromatic alcohols containing from about 1 to about 20 carbon atoms.
• Suitable alcohol moieties include those based on methanol, ethanol, propanol, isopropanol, butanol, isobutanol, stearyl alcohol, lauryl alcohol, phenol, benzyl alcohol, ethylene glycol, neopentyl glycol, CHDM, and diethylene glycol.
• step (b) and (c) of the present invention the polyester composition is respectively formed into a film or sheet and crystallization is induced.
• Inducing crystallization may be done either during or after forming the film or sheet.
• forming of the film or sheet occurs by melt extrusion or cast extrusion and inducing crystallization occurs after forming by stretching.
• forming of the film or sheet occurs by melt extrusion or cast extrusion and inducing crystallization occurs after forming by annealing at a temperature greater than the glass transition temperature of the film and less than melting temperature of the base copolyester.
• forming of the film or sheet and inducing crystallization occur together during step (b) by calendering or blown film extrusion.
• the most preferred embodiment of the present invention is a process for preparing a film or sheet comprising the steps of: (a) preparing a polyester composition comprising
• the base copolyester preferably comprises a diacid component comprising residues of at least 80 mole percent of a primary diacid selected from the group consisting of terephthalic acid, naphthalenedicarboxylic acid, 1 ,4-cyclohexanedicarboxylic acid, isophthalic acid and mixtures thereof and a diol component comprising residues of about 10 to about 40 mole percent 1 ,4-cyclohexanedimethanol and about 90 to 60 mole percent ethylene glycol, wherein the diacid component is based on 100 mole percent and the diol component is based on 100 mole percent.
• the plasticizer is preferably selected from the group consisting of neopentyl glycol dibenzoate, diethylene glycol di
• a film or sheet has a glass transition temperature below about 23°C, preferably below about 0°C, and a melting temperature greater than about 120°C, preferably greater than about 140°C; and comprises a polyester composition comprising (a) about 50 to about 95 weight percent of a base copolyester having a melting temperature of less than about 220°C and exhibiting more than about 1 percent crystallinity after annealing for 2000 minutes at a temperature of which the base copolyester has a maximum crystallization rate and (b) about 50 to about 5 weight percent of a plasticizer suitable for use with the base copolyester.
• base copolyester comprises a diacid component comprising residues of at least about 80 mole percent of a primary diacid selected from the group consisting of terephthalic acid, naphthalenedicarboxylic acid, 1,4-cyclohexanedicarboxylic acid, isophthalic acid and mixtures thereof and a diol component comprising residues of at about least 80 mole percent of at least one primary diol containing 2 to about 10 carbon atoms, wherein the diacid component is based on 100 mole percent and the diol component is based on 100 mole percent.
• a primary diacid selected from the group consisting of terephthalic acid, naphthalenedicarboxylic acid, 1,4-cyclohexanedicarboxylic acid, isophthalic acid and mixtures thereof
• a diol component comprising residues of at about least 80 mole percent of at least one primary diol containing 2 to about 10 carbon atoms
• the plasticizer presenting the film or sheet is present in an amount of from about 20 weight percent to about 50 weight percent.
• the plasticizer is preferably selected from one that dissolves a 5-mil thick film of the base copolyester to produce a clear solution at a temperature below 160°C. More preferably, the plasticizer is selected from one that has a solubility parameter in the range from about 9.5 to about 13.0 cal°' 5 crrf 1 " 5 .
• base copolyester comprises a diacid component comprising residues of at least about 80 mole percent of a primary diacid selected from the group consisting of terephthalic acid, naphthalenedicarboxylic acid, 1 ,4-cyclohexanedicarboxylic acid, isophthalic acid and mixtures thereof and a diol component comprising residues of about 10 to about 40 mole percent 1,4-cyclohexanedimethanol and about 60 to 90 mole percent ethylene glycol, wherein the diacid component is based on 100 mole percent and the diol component is based on 100 mole percent.
• the plasticizer is selected from the group consisting of neopentyl glycol dibenzoate, diethylene glycol dibenzoate, butyl benzyl phthalate; and texanol benzyl phthalate.
• a polyester which contains an acid component of 100 mole % terephthalic acid and a glycol component of 31 mole % 1 ,4- cyclohexanedimethanol and 69 mole % ethylene glycol arid has an IV of 0.76 dLJg, a weight average molecular weight of 40400 g/mol and a Tg of about 78°C, was pre-dried at 65°C for 12 hours in a dehumidified dryer and compounded with various plasticizers, as listed in Table 3, using a 30-mm Wemer-Pfleiderer 40:1 L/D co-rotating twin screw extruder.
• the extruded compositions were then formed into films having a thickness of 0.254 mm using a 25.4-mm Killion extruder fitted with a 152-mm film die.
• the films were subsequently annealed in a vacuum oven at 100°C for 90 minutes.
• Properties of the films including Tg, Tm, and weight average molecular weight before (Comparative Examples 1-4) and after (Illustrative Examples 5-8) the annealing process are summarized in Table 3.
• Examples 1 to 4 display a Tg below 23°C as measured by differential scanning calorimetry, DSC, at a heating rate of 20°C/min.
• Examples 1-4 show no Tm.
• DMTA Dynamic mechanical thermal analysis, DMTA, curves of Examples 1 to 4 are presented in Figure 1. All DMTA experiments were performed at an operating frequency of 16 Hz and a heating rate of 10°C/minute. Below the onset of the Tg, the compositions possess a high modulus indicative of a rigid material. During the transition from glass to rubber, the modulus falls precipitously. This region of the DMTA curve is commonly referred to as the leathery region because of the texture and feel of the material. At the end of the glass transition region, the DMTA curves display a short plateau that extends to between 50 and 80°C, which is followed by a drop in modulus due to viscous flow. This plateau defines the temperature regime where the composition is soft, flexible and rubber-like. Thus, the utility of Examples 1 to 4 is severely limited to a narrow range of temperatures above Tg defined by the short rubbery plateau.
• DMTA curves of Examples 5 to 8 are presented in Figure 2. Below the onset of Tg, the compositions possess a modulus similar to that of the non-annealed samples. The transition from glass to rubber in the annealed samples occurs over a broader range than in the non-annealed samples. 0 At the end of the glass transition region, the DMTA curves display a plateau that extends to about 150°C, approximately 70°C beyond the end of the rubbery plateau for the non-annealed samples. Consequently, the utility of Examples 5 to 8 now extends well beyond that for Examples 1 to 4. These results are totally unexpected. 5
• Example 9 The polyester composition of Example 9, with data summarized in Table 4, was prepared the same as Example 1.
• This example shows the properties of an extruded film that was subsequently subjected to a 3x3 biaxial stretch at 23°C to effect crystallization.
• the resulting film displays a Tg below 23°C and a Tm of 151°C. Both induced crystallization by annealing and stretching result in a film of the present invention that is soft and flexible at room temperature. 0
• Example 2 The same base copolyester of Example 1 was pre-dried at 65°C for 12 hours in a dehumidified dryer and compounded with various plasticizers, as listed in Table 4, using a 30-mm Werner-Pfleiderer 40:1 L/D co-rotating 5 twin screw extruder. Without additional drying, the extruded compositions were placed on a Farrell two-roll mill at a set roll temperature of 150°C. After 10 minutes, the polyester composition was removed from the mill and fed through a 3-roll vertical calendering stack with roll temperatures ranging from 110-120°C to produce 0.254-mm thick films. Properties of the films, 0 including Tg, Tm, and weight average molecular weight, are summarized as Illustrative Examples 10-13 in Table 4. Each example has a Tg below 23°C and a Tm between 150°C and 165°C.
• DMTA curves of Examples 9 to12 are presented in Figure 3. Each example displays a rubbery plateau that extends beyond 150°C. Thus, films are formed with a Tg below 23°C and rubber-like properties up to 150°C. These results are totally unexpected.
• Example 10-13 contain 0.50 wt % of a fatty acid ester release additive.
• Example 14
• the base copolyester of Example 1 was compounded with glycerol tribenzoate at 15 weight percent and 30 weight percent.
• the Tg of the 30 weight percent polyester composition was 32°C. Utilizing the Fox equation for predicting the Tg of polymer/plasticizer and polymer/polymer mixtures, a 40 weight percent glycerol tribenzoate polyester composition is expected to produce a mixture with a Tg below 23°C.
• Examples 15-19 A base copolyester, as shown for each Example 15-19 in Table 5, was pre-dried at 65°C for 12 hours in a dehumidified dryer and compounded with the plasticizer neopentyl glycol dibenzoate using a 30- mm Werner-Pfleiderer40:1 L/D co-rotating twin screw extruder. Without additional drying, the extruded compositions were placed on a Farrell two- roll mill at a set roll temperature of 150°C. After 10 minutes, the polyester composition was removed from the mill and fed through a 3-roll vertical calendering stack with roll temperatures ranging from 110-120°C to produce 0.254-mm thick films. Properties of the films, including Tg and Tm are summarized in Table 5.
• Examples 15-17 are illustrative examples of the present invention. While Examples 18 and 19 have a Tg greater than 23°C, the addition of more plasticizer would lower the Tg. In particular, utilizing the Fox equation, the Tg of a polyester composition utilizing the same base copolyester of Example 19 is predicted to be below 23°C at 22 weight percent neopentyl glycol dibenzoate plasticizer.

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