US20070093616A1 - Stable Polyamides For Simultaneous Solid Phase Polymerization of Polyesters and Polyamides - Google Patents

Stable Polyamides For Simultaneous Solid Phase Polymerization of Polyesters and Polyamides Download PDF

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US20070093616A1
US20070093616A1 US11/552,612 US55261206A US2007093616A1 US 20070093616 A1 US20070093616 A1 US 20070093616A1 US 55261206 A US55261206 A US 55261206A US 2007093616 A1 US2007093616 A1 US 2007093616A1
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polyester
polyamide
acid
compartmentalized
zone
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Joachim Strauch
Maria Scrivani
Simone Ferrero
Gianluca Ferrari
Douglas Callander
Arianna Giovannini
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APG Polytech LLC
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Joachim Strauch
Scrivani Maria T
Simone Ferrero
Gianluca Ferrari
Callander Douglas D
Arianna Giovannini
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Application filed by Joachim Strauch, Scrivani Maria T, Simone Ferrero, Gianluca Ferrari, Callander Douglas D, Arianna Giovannini filed Critical Joachim Strauch
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29B—PREPARATION OR PRETREATMENT OF THE MATERIAL TO BE SHAPED; MAKING GRANULES OR PREFORMS; RECOVERY OF PLASTICS OR OTHER CONSTITUENTS OF WASTE MATERIAL CONTAINING PLASTICS
    • B29B9/00—Making granules
    • B29B9/12—Making granules characterised by structure or composition
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29B—PREPARATION OR PRETREATMENT OF THE MATERIAL TO BE SHAPED; MAKING GRANULES OR PREFORMS; RECOVERY OF PLASTICS OR OTHER CONSTITUENTS OF WASTE MATERIAL CONTAINING PLASTICS
    • B29B13/00—Conditioning or physical treatment of the material to be shaped
    • B29B13/02—Conditioning or physical treatment of the material to be shaped by heating
    • B29B13/021—Heat treatment of powders
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29B—PREPARATION OR PRETREATMENT OF THE MATERIAL TO BE SHAPED; MAKING GRANULES OR PREFORMS; RECOVERY OF PLASTICS OR OTHER CONSTITUENTS OF WASTE MATERIAL CONTAINING PLASTICS
    • B29B9/00—Making granules
    • B29B9/02—Making granules by dividing preformed material
    • B29B9/06—Making granules by dividing preformed material in the form of filamentary material, e.g. combined with extrusion
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G69/00—Macromolecular compounds obtained by reactions forming a carboxylic amide link in the main chain of the macromolecule
    • C08G69/02—Polyamides derived from amino-carboxylic acids or from polyamines and polycarboxylic acids
    • C08G69/36—Polyamides derived from amino-carboxylic acids or from polyamines and polycarboxylic acids derived from amino acids, polyamines and polycarboxylic acids
    • 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
    • C08J3/00—Processes of treating or compounding macromolecular substances
    • C08J3/005—Processes for mixing polymers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L67/00—Compositions of polyesters obtained by reactions forming a carboxylic ester link in the main chain; Compositions of derivatives of such polymers
    • C08L67/02—Polyesters derived from dicarboxylic acids and dihydroxy compounds
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L77/00—Compositions of polyamides obtained by reactions forming a carboxylic amide link in the main chain; Compositions of derivatives of such polymers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L77/00—Compositions of polyamides obtained by reactions forming a carboxylic amide link in the main chain; Compositions of derivatives of such polymers
    • C08L77/02—Polyamides derived from omega-amino carboxylic acids or from lactams thereof
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L77/00—Compositions of polyamides obtained by reactions forming a carboxylic amide link in the main chain; Compositions of derivatives of such polymers
    • C08L77/06—Polyamides derived from polyamines and polycarboxylic acids
    • 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
    • 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
    • B29K2077/00—Use of PA, i.e. polyamides, e.g. polyesteramides or derivatives thereof, as moulding material
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G63/00—Macromolecular compounds obtained by reactions forming a carboxylic ester link in the main chain of the macromolecule
    • C08G63/78—Preparation processes
    • C08G63/80—Solid-state polycondensation
    • 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
    • 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
    • C08K5/36—Sulfur-, selenium-, or tellurium-containing compounds
    • C08K5/41—Compounds containing sulfur bound to oxygen
    • C08K5/42—Sulfonic acids; Derivatives thereof
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/13—Hollow or container type article [e.g., tube, vase, etc.]
    • Y10T428/1352—Polymer or resin containing [i.e., natural or synthetic]

Definitions

  • This invention relates to polyamides suitable for the simultaneous solid phase polymerization of polyesters and polyamides at polyester conditions.
  • Multi-component articles made from thermoplastic and thermoset materials are generally manufactured with a final melt-mixing extruder that homogenously combines the various components into an article such as a sheet, film, fiber, a bottle or an injection molded part, frequently called a preform.
  • the article, particularly the preform is often further processed to make another article such as a bottle, tray, jar, or bag.
  • Solid phase polymerization efficiently increases the number average molecular weight of both polyesters and polyamides.
  • the increase in number average molecular weight can be measured with many techniques such as inherent viscosity (Inh. V.) and intrinsic viscosity (I.V.), relative viscosity (R.V.), and the total number of end groups (TEG).
  • Inh. V. inherent viscosity
  • I.V. intrinsic viscosity
  • R.V. relative viscosity
  • TOG total number of end groups
  • the thermal processing can occur from 40° C. to a temperature slightly less than the temperature at which the pellet becomes liquid, such as 1° C., or for more typically for commercial reasons, 5° C. below the temperature at which the pellet becomes liquid.
  • U.S. Pat. No. 5,340,884 advocates combining the polyester and polyamide at the first cutting step after polycondensation to eliminate additional and/or subsequent extrusion and cutting steps. But, U.S. Pat. No. 5,340,884 also cautions against blending the polyamide and polyester as they are removed from the polycondensation reactor if the polyester/polyamide blend will be subjected to further thermal processing such as solid state polymerization. Subsequent thermal processing may create undesirable color and/or haze and alter the molecular weight of the polyamide during extended time at elevated temperatures.
  • U.S. Pat. No. 6,238,233 teaches blending acid terminated polyamides with polyester. However, U.S. Pat. No. 6,238,233 cautions against blending the molten polyester with acid terminated polyamide as it is removed from the polycondensation reactor before it is pelletized if the polyester/polyamide blend will be subjected to solid state [phase] polymerization since undesirable color and/or haze may develop during extended time at elevated temperatures.
  • WO 2005/110694 A1 teaches the use of the compartmentalized pellet to reduce the color caused by simultaneously thermally treating a polyester-polyamide blend.
  • the polyester-polyamide composition does not exhibit increased color during thermal processing when the majority of the polyester is placed in one compartment or zone of the pellet and the majority of the polyamide is placed in another compartment or zone prior to thermal processing.
  • WO 2005/110694 A1 acknowledges that certain compounds are not stable at high processing temperatures and extended processing times.
  • WO 2005/110694 A1 teaches to use a reaction enhancer or raise the starting molecular weight to allow the pellet to solid phase polymerized at a lower temperature and shorter time if one of the components cannot withstand the higher process temperatures. These approaches increase the cost to thermally process the materials together.
  • a resin composition comprising a polyester selected from the group consisting of crystallizable polyesters that have at least 85% of the crystallizable polyester acid moieties derived from the group consisting of terephthalic acid, 2,6 naphthalene dicarboxylic acid and their diesters and a polyamide comprising a residue selected from the group consisting of the repeating unit of amino caproic acid and the repeating unit of A-D, wherein A is the residue of a dicarboxylic acid comprising adipic acid, isophthalic acid, terephthalic acid, 1,4-cyclohexanedicarboxylic acid, or naphthalenedicarboxylic acid, or a mixture thereof, and D is a residue of a diamine comprising m-xylylene diamine, p-xylylene diamine, hexamethylene diamine, ethylene diamine, or 1,4 cyclohexanedimethylamine, or a mixture thereof, wherein
  • the resin composition can have at least 90% of the crystallizable polyester's acid moieties derived from terephthalic acid and at least 90% of the crystallizable polyester's glycol moieties are derived from ethylene glycol.
  • a preferred polyamide, MXD6 is also disclosed.
  • the composition may exist as a resin pellet with the polyamide dispersed into the polyester or as a compartmentalized pellet comprising a first compartmentalized zone and a second compartmentalized zone, wherein the first compartmentalized zone is comprised of the polyester and the second compartmentalized zone is comprised of the polyamide.
  • a process for solid phase polymerizing a polyester and a polyamide at the same temperature for the same amount of time comprises the steps of A) Selecting a polyester from the group consisting of crystallizable polyesters that have at least 85% of the crystallizable polyester acid moieties derived from the group consisting of terephthalic acid, 2,6 naphthalene dicarboxylic acid and their diesters and a polyamide comprising a residue selected from the group consisting of the repeating unit of amino caproic acid and the repeating unit of A-D, wherein A is the residue of a dicarboxylic acid comprising adipic acid, isophthalic acid, terephthalic acid, 1,4-cyclohexanedicarboxylic acid, or naphthalenedicarboxylic acid, or a mixture thereof, and D is a residue of a diamine comprising m-xylylene diamine, p-xylylene diamine, hexamethylene diamine,
  • crystallizable polyester's acid moieties can be derived from terephthalic acid and 90% of the crystallizable polyester's glycol moieties can be derived from ethylene glycol.
  • the preferred polyamide for the process is MXD6 nylon.
  • the polyamide and polyester may be combined into the pellets so that the polyamide is dispersed into the polyester or combined into compartmentalized pellets comprising a first compartmentalized zone and a second compartmentalized zone, wherein the first compartmentalized zone is comprised of the polyester and the second compartmentalized zone is comprised of the polyamide. It is further disclosed to heat the pellets to a temperature in the range of 165° C. and 235° C. wherein at least 90% of the crystallizable polyester's acid moieties are derived from terephthalic acid and at least 90% of crystallizable polyester's glycol moieties are derived from ethylene glycol. Also disclosed is that the crystallizable polyester comprises lithium sulfoisophthalate.
  • FIG. 1 depicts a resin pellet with two compartments or zones in the core-sheath configuration.
  • FIG. 2 depicts a resin pellet with two compartments or zones in the core-sheath configuration where the core is encapsulated, surrounded, or enclosed by an outer sheath layer.
  • FIG. 3 depicts a resin pellet with three compartments or zones in a multi-layered or sandwich configuration.
  • FIG. 4 depicts a resin pellet of three compartmentalized zones configured in two concentric layers surrounding a core.
  • This specification discloses the characteristics of a polyamide and crystallizable polyester that allow the practitioner to solid phase polymerize both the polyamide and crystallizable polyester in the same vessel under the same conditions without significantly negatively impacting the properties of the resulting blend.
  • Solid phase polymerization is an important industrial process. It efficiently increases the number average molecular weight of both polyesters and polyamides.
  • the increase in number average molecular weight can be measured with many techniques such as intrinsic viscosity (I.V.), relative viscosity (R.V.), and the total number of end groups (TEG).
  • I.V. intrinsic viscosity
  • R.V. relative viscosity
  • TAG total number of end groups
  • the pellets are exposed to temperatures less than the temperature at which the pellets become liquid. This temperature exposure occurs in the presence of a driving force such as an inert gas or vacuum.
  • the by-products of the polymerization reaction are removed from the pellet thus forcing an equilibrium increase in the molecular weight of the polymer.
  • the solid phase polymerization (SSP) conditions for a crystallizable polyester-polyamide combination generally mirror the solid phase polymerization conditions for crystallizable polyester and preferably include a temperature of from about 200° C. to about 235° C., and more preferably from about 215° C. to about 235° C.
  • the solid phase polymerization is carried out for a time sufficient to raise the molecular weight of one or more of the components to the desired level, which will depend upon the application and initial intrinsic viscosity.
  • the preferred molecular weight of a polyester used to make bottles generally corresponds to an intrinsic viscosity (I.V.) from about 0.68 to about 0.88 deciliter/gram, as determined by the methods described in the methods section.
  • the time required to reach this molecular weight may range from about 8 to about 45 hours.
  • Typical increases in I.V. of the crystallizable polyester are at least 0.05 dl/g, with increases of 0.2 to 0.4 dl/g being more typical.
  • a major cause of the gel formation is the presence of triamine in the polyamide. While not to be bound by any theory, it is believed that the triamine is formed by the reaction of the two amino end groups with each other, releasing —NH 3 to form a tertiary amine, or triamine.
  • the starting compounds are shown as EQ-1 which form the product of EQ-2 Where R ⁇ NH 2 or the continuing polymer chain. EQ-2 will further react with EQ-3 Where R′ ⁇ OH or the continuing polymer chain to form EQ-4. Which is believed to be the branched gel.
  • the amount of tertiary amine in the polyamide can be indirectly measured by subjecting the polyamide to hydrolysis as described in the test method section. Under hydrolysis, the tertiary amine will reduce to the compound of the following formula EQ-5.
  • the claimed polyamide is characterized as having a triamine content after hydrolysis less than 0.22 weight percent which is the amount of the compound of EQ-5 in the polyamide sample divided by the weight of the polyamide sample, expressed in percent.
  • triamine content and “triamine content after hydrolysis”, as used in the specification and claims, mean the amount of material of EQ-5 after hydrolysis of the polyamide expressed as a weight percent of the total amount of the polyamide before hydrolysis. If the triamine content is expressed without a unit, then weight percent is always assumed. For example, a triamine content of 0.22 is a triamine content of 0.22 weight percent, or 0.22%.
  • the polyamide can be solid phase polymerized at polyester temperatures without producing gels.
  • the data demonstrate that both the pellets of polyamide homogenously dispersed in polyester and the pellets of the compartmentalized pellet with one compartmentalized zone comprising polyester and another compartmentalized zone comprising polyamide will benefit from the polyamide with low, or preferably, no triamine content. Because the compartmentalized pellet keeps the polyamide and polyester separate, the gels which form in the polyamide are large and visibly apparent. It is believed that the size of the polyamide domains in the homogeneously dispersed pellet is so small that the gels which are formed are observed primarily as increased haze.
  • the shift in colour still occurs in the homogenously dispersed pellet when the polyamide with the low triamine content is thermally treated. Therefore, the best results are achieved when the polyamide with the low triamine content and the crystallizable polyester are solid phase polymerized in the compartmentalized pellet structure.
  • the triamine content after hydrolysis can be measured using the hydrolysis technique described in the methods section.
  • One way to keep the triamine content low is to run the reaction in the presence of excess amounts of dicarboxylic acid.
  • Polyamides suitable for this invention can be described as comprising the repeating unit amino caproic acid or A-D, wherein A is the residue of a dicarboxylic acid comprising adipic acid, isophthalic acid, terephthalic acid, 1,4-cyclohexanedicarboxylic acid, or naphthalenedicarboxylic acid, or a mixture thereof, and D is a residue of a diamine comprising m-xylylene diamine, p-xylylene diamine, hexamethylene diamine, ethylene diamine, or 1,4 cyclohexanedimethylamine, or a mixture thereof.
  • These polyamides can range in number average molecular weight from 2000 to 60,000 as measured by end-group titration.
  • Relative Viscosity is used to determine molecular weight as it is not subject to different end groups that may occur as a result of side reactions during the manufacturing process.
  • the Relative Viscosity selected should be one which meets the required levels when the polyamide and polyester are melt blended. Generally this is in the range of 1.0 to 3.0, with the most desirable properties obtained when the Relative Viscosity is between 1.4 and 2.0.
  • polyamides can also be described as comprising a reaction product selected from the group consisting of the reaction of amino caproic acid with itself and the reaction product of a residue of dicarboxylic acid comprising adipic acid, isophthalic acid, terephthalic acid, 1,4-cyclohexanedicarboxylic acid, or naphthalenedicarboxylic acid with a residue of a diamine comprising m-xylylene diamine, p-xylylene diamine, hexamethylene diamine, ethylene diamine, or 1,4 cyclohexanedimethylamine.
  • the reaction product of the residues of sebacic acid with hexamethylene diamine is nylon 6.10 and the reaction product of the residues of adipic acid and hexamethylene diamine is nylon 6.6.
  • Nylon 6.12 is another nylon which benefits from the invention.
  • Nylon 6 is a special type of polyamide which is made by the opening of caprolactam and then polymerizing the resulting amino caproic acid which has a formula of H 2 N—(CH 2 ) 5 —COOH.
  • the preferred polyamides are the reaction product of the residues of adipic acid and m-xylylene diamine, known as poly-m-xylylene adipamide. This product is commercially known as MXD6 or nylon MXD6 and can be purchased from Mitsubishi Gas Chemical Company, Japan.
  • the weight percent of triamine content after hydrolysis of the polyamide must be less than 0.22, preferably less than 0.21, with less than 0.15 and even less than 0.10 the most preferred levels.
  • the polyamide have an unbalanced number of amino and acid end groups. It has been discovered that the polyamide is more stable during solid phase polymerization when the end groups are highly out of balance. By keeping the ratio severely unbalanced, the solid state polymerization rate of the polyamide is very slow, thus limiting the molecular weight increase of the polyamide. This means that during solid phase polymerization, the polyester can undergo an increase in molecular weight while the relative viscosity of the polyamide remains relatively unchanged.
  • the carboxyl content will be less than 20 percent of the total number of end groups or greater than 80% of the total number of end groups.
  • the practioner should keep the number of carboxyl end groups content less than 10% or greater than 90% of the total number of end groups.
  • Another way to express this characterization is that the carboxyl content is outside the range of 20 to 80 percent of the total number of ends. This means the carboxyl content cannot be between 20 and 80 percent, but could be 15 or 85 percent.
  • the preferred polyamide is MXD6 made in any of the following manners.
  • All the processes use adipic acid and meta-xylylenediamine where the molar ratio of adipic acid and meta-xylylenediamine can be varied in the range of 1.5:1 to 1.001:1, preferably 1.2:1 to 1.005:1, especially 1.1:1 to 1.007:1, especially preferred 1.05:1 to 1.01:1.
  • One preferred process is a batch process using a stirred steel autoclave operating at a pressure between 2 and 10 bars, preferably between 3 and 8 bars and especially preferred between 4 and 6 bars.
  • a two step pressure profile is applied.
  • the raw materials are placed in the vessel and then heated to 120° C. inside the autoclave. After a reaching a pressure of 2 bars, water is distilled off, until a ca. 90 w. % mixture is obtained. During distillation, the temperature is increased to 155-165° C. The mixture is then further heated until the desired pressure of 4 bars is reached. At 4 bars the remaining water is distilled off and temperature is increased to 245-250° C. Afterwards the pressure is reduced to atmospheric pressure.
  • the temperature of the contents inside the autoclave should not exceed 265° C. during the whole condensation process.
  • the relative viscosity measured after pelletizing is in the range between 1.45 and 1.70.
  • the polyamide may be made in a continuous process by heating salt solutions of adipic acid and meta-xylylene diamine at a temperature of 210 to 330° C., preferentially 250 to 300° C., more preferably 260 to 280° C., then preferably separating the prepolymer batchwise or preferably in a continuous way and recycling the separated meta-xylylene diamine.
  • the prepolymer is then kept under a pressure between 1 and 20 bar, preferably between 1.5 and 15 bar, and most preferably between 4 and 6 bar at a temperature between 230 to 330° C., especially preferably between 260 to 280° C. and polycondensed.
  • Another process to make the polyamide comprises heating a salt solution of the diamine and the dicarboxylic acid under a pressure between 2 and 10 bar, preferably 4 and 6 bar within a residence time of 60 seconds, with at least 95% degree of conversion and a maximum of 7 weight percent water.
  • This polymer can be achieved by running the salt solution through a in sectioned tubular designed evaporation zone, in which by heating and water evaporation a two phase flow is developed; thereby driving the major amount of solution water into the gas phase.
  • the used aqueous solutions have normally a monomer content of 30 to 70 w. %, preferably 45 to 65 w. %.
  • An especially preferred process consists of running the aqueous salt solution with a temperature of 50 to 100° C. batchwise or preferably continuously into an evaporation zone, where the salt solution is heated under a pressure of 2 to 10 bar, preferably 4 to 6 bar to a temperature of 250 to 300 ° C., preferably 260 to 280° C.
  • the residence time in the evaporation zone is normally 1 to 300 seconds, preferably 30 to 120 seconds and especially preferred 30 to 60 seconds.
  • the conversion ranges from 80 to 100%, preferably 90 to 99.5%, especially preferred 95 to 99%, particularly 96 to 98 % and, depending on the pressure used, the water content is normally 0.01 to 10 w. %, preferably 0.1 to 5 w.
  • the evaporation zone is favourably designed as a pack of tubes, in which the diameter of the single tubes is periodically tubular or “split shaped” formed. Further it was proved to be advantageous to run the mixture of prepolymer and steam before separating the phases through a tubular “substance exchange zone”, which is modified with fixtures. Here the pressure and temperature conditions of the evaporation zone are kept constant.
  • the fixtures for example, are carrier materials like Raschig rings, metal rings and especially carrier material made of wire gauze to create a large surface area. In this design, the phases, prepolymer and steam, come into close contact. This reduces the amount of meta-xylylene diamine set free by the steam.
  • the residence time in this “substance exchange zone” is normally 1 to 5 minutes.
  • the two phase mixture of steam and prepolymer is separated after leaving the evaporation zone and “substance exchange zone” respectively.
  • the generated vapours contain water and traces of meta-xylylenediamine, which is liberated by the evaporation of the water. Thereby only extremely small amounts of meta-xylylene diamine are contained in the gas phase. ( ⁇ 0.1 w. % based on the polymer throughput).
  • the vapours can be fed into a column and rectified to regain the meta-xylylene diamine. Appropriate columns are carrier material columns, bubble-cap columns or sieve-plate columns with 5 to 15 theoretical plates. The column is run under the same pressure conditions as the evaporation zone. Preferably the rectified meta-xylylene diamine is fed back to the polymerization zone.
  • the obtained melt can be polycondensed at a temperature between 245 and 285° C., preferably between 255 and 275° C. and a pressure from 2 to 10 bar, especially from 4 to 6 bar.
  • the obtained polyamide can be exposed to a discharge zone during simultaneous removal of rest water.
  • Appropriate discharge zones are for example extruders.
  • the melt, which is now liberated from water, can be pelletized. After polycondensation, the melt can be treated in any one of the well known post-treatments, for example, under water pelletizing (spherical and cylindrical chips) or strand pelletizing.
  • the obtained resin can also be subjected to an extraction, which can be performed batchwise or continuously. Water, C 1 -C 8 -alkanols like methanol or ethanol can be used as extractants. Water is preferred.
  • the polyamide is pelletized to spherical chips using under water pelletizing.
  • the relative viscosity after leaving the extruder is in the range of about 1.45 to about 1.55.
  • the extracted polyamide can then undergo a solid phase or solid state polymerization (SSP) for final adjustment of the relative viscosity.
  • SSP solid phase or solid state polymerization
  • This can be performed under vacuum or under an inert gas as nitrogen or Argon, preferably nitrogen.
  • the temperature can vary over a range, normally between 120 and 230° C., preferably between 130 and 210° C., with 140 to 190° C. especially preferred.
  • the final relative viscosities after SSP are between 1.55 and 2.00, preferably between 1.60 to 1.9 and especially between 1.65 and 1.75.
  • the water content is usually less than 250 ppm.
  • the polyesters suitable for this invention are the crystallizable polyesters.
  • crystallizable means that the polyester, such as polyethylene terephthalate, polyethylene naphthalate or their copolymers can become semi-crystalline, either through orientation or heat induced crystallinity. It is well known that no plastic is completely crystalline and that the crystalline forms are more accurately described as semi-crystalline.
  • semi-crystalline is well known in the prior art and is meant to describe a polymer that exhibits X-ray patterns that have sharp features of crystalline regions and diffuse features characteristic of amorphous regions. It is also well known in the art that semi-crystalline should be distinguished from the pure crystalline and amorphous states.
  • Differential Scanning Calorimetry can be used to measure the amount of crystallinity.
  • Typical crystallinity levels range from 5 to as high 65 percent depending upon the type of thermal treatment and nucleation techniques used.
  • a crystallizable polyester will be considered amorphous, but still crystallizable, when it has less than 5% crystallinity.
  • a polyester is crystallizable, that is, capable of becoming semi-crystalline, when the number of moles of the monomers beyond the first acid and first diol is less than 15% of the total number of moles of acids and diols in the polymer.
  • the crystallizable polyester can therefore generally be described as comprising the derivative of a first acid and a first diol, wherein the number of moles of the first acid plus the number of moles of the first diol divided the total number of moles of acids and glycols in the polymer is at least 85%.
  • polyethylene isophthalate is derived from 100 moles of isophthalic acid reacted with 100 moles ethylene glycol, yet is an amorphous polymer. This polymer is excluded from the crystallizable polyesters because it is not crystallizable.
  • the preferred crystallizable polyester more specifically comprises the derivative of a first acid selected from the group consisting of terephthalic acid, 2,6 naphthalene dicarboxylic acid, and a first diol selected from the group consisting of ethylene glycol, 1,4 butane diol and 1,3 propane diol, wherein the number of moles of the first acid plus the number of moles of the first diol divided the total number of moles of acids and glycols in the polymer is at least 85%.
  • a first acid selected from the group consisting of terephthalic acid, 2,6 naphthalene dicarboxylic acid
  • a first diol selected from the group consisting of ethylene glycol, 1,4 butane diol and 1,3 propane diol
  • the measurement of the total amount of acids and glycols reacted into the polymer should be done upon the polymer after polymerization. Determination of the species and the relative amount of each species is done by depolymerizing the polymer into its respective monomers and quantifying the resultant monomers via gas chromatography.
  • a copolymer of polyethylene terephthalate or polyethylene terephthalate copolymer is also expressed as copolyethylene terephthalate.
  • the class of polyesters known as the polyethylene terephthalates or PET are those polyesters wherein at least 85% of the repeating acid units based upon the total number of acid units are derived from terephthalic acid or the diester of terephthalic acid, at least 85% of the repeating glycol units based upon the total number of glycol units are derived from ethylene glycol and the remainder of the acid and/or glycol units are derived from at least one other different repeating unit.
  • a third, and subsequent repeating unit could be, for example, derived from isophthalic acid, 2,6 naphthalene dicarboxylic acid, cyclohexanedimethanol, 1,4 butane diol or 1,3 propane diol.
  • the crystallizable polyesters may be prepared by melt phase polymerization involving the reaction of a diol with a dicarboxylic acid, or its corresponding diester.
  • Various copolymers resulting from use of multiple diols and diacids may also be used.
  • Polymers containing repeating units of only one chemical composition are homopolymers.
  • Polymers with two or more chemically different repeat units in the same macromolecule are termed copolymers.
  • a polymer of the terephthalate, isophthalate and 2,6 naphthalate moieties reacted with ethylene glycol, diethylene glycol and cyclohexanedimethanol contains six distinct monomers and is considered a copolymer.
  • copolymers include reacting one or more diols with one or more diacids, and are sometimes also referred to as terpolymers. Additionally, randomization of the monomers is not necessary.
  • a copolymer or terpolymer also refers to a polymer with different monomers be they in block or random distribution.
  • Suitable dicarboxylic acids include those comprising from about 6 to about 40 carbon atoms.
  • Specific dicarboxylic acids include, but are not limited to, terephthalic acid, isophthalic acid, naphthalene 2,6-dicarboxylic acid, cyclohexanedicarboxylic acid, cyclohexanediacetic acid, diphenyl-4,4′-dicarboxylic acid, 1,3-phenylenedioxydiacetic acid, 1,2-phenylenedioxydiacetic acid, 1,4-phenylenedioxydiacetic acid, succinic acid, glutaric acid, adipic acid, azelaic acid, sebacic acid, and the like.
  • Specific esters include, but are not limited to, phthalic esters and naphthalic diesters.
  • polyester ionomers such as metallo-sulfonates.
  • these ionomer include but are not limited to the sulfonated isophthalate salts of lithium, sodium, zinc, sulfur, and phosphorous.
  • acids or esters may be reacted with an aliphatic diol having from about 2 to about 10 carbon atoms, a cycloaliphatic diol having from about 7 to about 14 carbon atoms, an aromatic diol having from about 6 to about 15 carbon atoms, or a glycol ether having from 4 to 10 carbon atoms.
  • Suitable diols include, but are not limited to 1,4-butenediol, trimethylene glycol, 1,6-hexanediol, 1,4-cyclohexanedimethanol, diethylene glycol, resorcinol, and hydroquinone.
  • Polyfunctional comonomers can also be used, typically in amounts of from about 0.1 to about 3 mole percent. Suitable comonomers include, but are not limited to, trimellitic anhydride, trimethylopropane, pyromellitic dianhydride (PMDA), and pentaerythritol. Polyester-forming polyacids or polyols can also be used.
  • PET polyethylene terephthalate
  • PEN polyethylene naphthalate
  • PBT polybutylene terephthalate
  • PET copolymers, PEN copolymers, and PBT copolymers are also preferred.
  • PET with combinations of moieties derived from isophthalic acid or its diester, 2,6 naphthalene dicarboxylic acid or its diester, and/or cyclohexane dimethanol. These mole ratios would be the 98:2:98:2 terephthalate:isophthalate:ethylene glycol:diethylene glycol is a preferred crystallizable polyester for this invention.
  • the esterification or polycondensation reaction of the carboxylic acid or ester with ethylene glycol typically takes place in the presence of a catalyst.
  • Suitable catalysts include, but are not limited to, antimony oxide, antimony triacetate, antimony ethylene glycolate, organo-magnesium, tin oxide, titanium alkoxides, dibutyl tin dilaurate, and germanium oxide. These catalysts may be used in combination with zinc, manganese, or magnesium acetates or benzoates. Catalysts comprising antimony are preferred.
  • the crystallizable polyester have an I.V. prior to solid phase polymerization of between 0.2 and 0.95 dl/g.
  • a film forming crystallizable polyester of at least 0.45 dl/g, an intermediate feed I.V. of 0.49 to 0.59 dl/g, more preferably 0.52 to 0.56 dl/g.
  • the pellet could also comprise a crystallizable polyester bottle resin of feed I.V. ranging from 0.59 to 0.75 dl/g, more preferably 0.61 to 0.64 dl/g.
  • the typical I.V. increase during solid phase polymerization is at least 0.04 dl/g, but can be as high 0.2 or even as high as 0.4 dl/g.
  • Polytrimethylene terephthalate is another preferred crystallizable polyester. It can be prepared by, for example, reacting 1,3-propanediol with at least one aromatic diacid or alkyl ester thereof.
  • Preferred diacids and alkyl esters include terephthalic acid (TPA) or dimethyl terephthalate (DMT). Accordingly, the PTT preferably has at least about 85 mole percent of its acid moieties derived from TPA or DMT.
  • Other diols which may be copolymerized in such a polyester include, for example, ethylene glycol, diethylene glycol, 1,4-cyclohexane dimethanol, and 1,4-butanediol.
  • Isophthalic acid and sebacic acid are examples of aromatic and aliphatic acids that may be used simultaneously to make a copolymer.
  • Preferred catalysts for preparing PTT include titanium and zirconium compounds.
  • Suitable catalytic titanium compounds include, but are not limited to, titanium alkylates and their derivative, titanium complex salts, titanium complexes with hydroxycarboxylic acids, titanium dioxide-silicon dioxide-co-precipitates, and hydrated alkaline-containing titanium dioxide.
  • Specific examples include tetra-(2-ethylhexyl)-titanate, tetrastearyl titanate, diisopropoxy-bis(acetyl-acetonato)-titanium, di-n-butoxy-bis(triethanolaminato)-titanium, tributylmonoacetyltitanate, triisopropyl monoacetyltitanate, tetrabenzoic acid titanate, alkali titanium oxalates and malonates, potassium hexafluorotitanate, and titanium complexes with tartaric acid, citric acid or lactic acid.
  • Preferred catalytic titanium compounds are titanium tetrabutylate and titanium tetraisopropylate.
  • the corresponding zirconium compounds may also be used.
  • the preferred polyester of this invention may also contain small amounts of phosphorous compounds, such as phosphates, and a catalyst such as a cobalt compound, that tends to impart a blue hue.
  • phosphorous compounds such as phosphates
  • a catalyst such as a cobalt compound
  • Other agents that may be included are infrared absorbers such as carbon black, graphite, and various iron compounds.
  • the polyester may also be void of cobalt.
  • the melt phase polymerization described above may be followed by a crystallization step and then a solid phase polymerization (SSP) step to increase the molecular weight, as measured by Intrinsic Viscosity, necessary for bottle manufacture.
  • SSP solid phase polymerization
  • the crystallization and polymerization can be performed in a tumbler dryer reaction in a batch-type system.
  • the crystallization and polymerization can be accomplished in a continuous solid phase process whereby the polymer flows from one vessel to another after its predetermined thermal treatment in each vessel.
  • the crystallization conditions for PET preferably include a temperature of from about 100° C. to about 150° C.
  • Typical thermal processing operations for crystallizing PET increase the crystallinity of the PET in the pellet by at least 5 percent.
  • the solid phase polymerization conditions preferably include a temperature of from about 200° C. to about 1° C. less than the melting point of the crystallized polyester.
  • the solid phase polymerization is carried out for a time sufficient to raise the molecular weight to the desired level, which will depend upon the application and initial intrinsic viscosity.
  • the preferred molecular weight corresponds to an intrinsic viscosity from about 0.54 to about 0.88 deciliter/gram, as determined by the methods described in the methods section.
  • the time required to reach this molecular weight may range from about 8 to about 45 hours.
  • Typical increases in I.V. are at least 0.04 dl/g, with increases in the range of 0.2 to 0.4 dl/g being more typical.
  • thermoplastic polymer matrix of the present invention may comprise recycled polyester or materials derived from recycled polyester, such as polyester monomers, catalysts, and oligomers.
  • the polyester-polyamide composition may also include a compatibilizer which increases the dispersion of the polyamide into the polyester.
  • a compatibilizer which increases the dispersion of the polyamide into the polyester. Examples of such compatibilizers are found in U.S. Patent Application 2004/0013833 A1, the teachings of which are incorporated in their entirety, describes isophthalic acid (IPA)-modified PET and PET ionomers as compatibilizers.
  • the preferred compatibilizer of U.S. Patent Application 2004/0013833 A1 is an ionic compatibilizer, preferably a copolyester, containing a metal sulfonate salt group.
  • the metal ion of the sulfonate salt may be Na+, Li+, K+, Zn++, Mn++, and Ca++.
  • the sulfonate salt group is often attached to an aromatic nucleus such as a benzene, naphthalene, diphenyl, oxydiphenyl, sulfonyldiphenyl, or methylenediphenyl nucleus, it can equally be attached to a non-aromatic nucleus such as sulfonated polystyrene.
  • the aromatic acid nucleus is sulfoisophthalic acid, sulfoterephthalic acid, sulfoisophthalic acid, 4-sulfonaphthalene, 2,7 dicarboxylic acid, and their esters.
  • the preferred range of the ionic compatibilizer is 0.05 to 2.0 mole percent by weight of the respective acid or glycol moiety.
  • the compatibilizer may exist as a third component in the composition or alternatively, the ionic compatibilizer can be polymerized into the molecular chain of the polyester or polyamide resin. If the compatibilizer is copolymerized into the polyester matrix, the moles of ionic compatibilizer are included in the total moles the acid and the glycol. For example, copolymerizing 0.5 moles of lithium sulfoisophthalic acid into the polyester molecule would mean there were 99.5 moles of terephthalic acid, 0.5 moles of lithium sulfoisophthalic acid and 98 moles of ethylene glycol and 2 moles of diethylene glycol for every 200 moles of total monomers in the polymer.
  • the compartmentalized pellet taught by WO 2005/110694 A1 the teachings of which are incorporated in their entirety should be used and is therefore the preferred structure.
  • a special embodiment of is an inner compartment surrounded by an outer compartment, wherein the polyamide with low triamine content is in the core It should be understood that in such an embodiment, the temperature exposure may melt or liquefy the material in the encapsulated core without melting the skin surrounding the core. This pellet with a liquefied inner compartment and solid skin is not considered a liquid pellet.
  • the core-sheath structure is obtained using two extruders. If a third material in another zone is desired, an additional extruder is required.
  • the first extruder supplies the liquid feed forming the core material which is linearly extruded at the center of the strand.
  • the sheath material is extruded in the second extruder into the sheath layer which concentrically covers the core.
  • U.S. Pat. No. 6,669,986 discloses a multiple hole die apparatus to manufacture a core-sheath pellet.
  • FIG. 1 depicts the core-sheath compartmentalized pellet having a core 1 which is substantially covered by a sheath 2 .
  • the polyester is extruded into the outer sheath 2 and the polyamide with low triamine content (preferably MXD6) extruded into the core 1 .
  • the strand could consist of more than two annular concentric layers, such as FIG. 4 . This could be accomplished by using another extruder and different die.
  • the first step is to extrude a multilayer strand.
  • One component is extruded in the center of the pellet and the other component is extruded around the center component.
  • the extruded multilayer strand is cut by a pelletizer before or after it is cooled, as required, and formed into multilayer pellets.
  • the strand is then cooled by conventional methods.
  • the strand can be immersed in a water tank with cool water.
  • the water-cooled multilayer strand is preferably sent to the pelletizer after removing surface moisture, often done by a spin dryer.
  • the pelletizer cuts the multilayer strand into a specified length by driving a rotary knife, or the like. By cutting the multilayer strand as it is, double columnar form multilayer pellets comprising the core material and the sheath material are obtained.
  • multilayer or compartmentalized pellets with an outside diameter of about 2 to 8 mm are manufactured.
  • the present invention is also not limited to pellets made from strands.
  • the thermoplastic polymers can be cast into layered sheets that are then cut in a cube form as well.
  • the minimum structure is two layers, but the preferred structure for a cast structure of this invention is depicted in FIG. 3 .
  • the sandwich or layered construction there are at least three layers wherein the middle layer 33 is sandwiched between a first outer layer 31 and a second outer layer 32 .
  • the compartmentalized zones can be classified as a first compartmentalized zone, a second compartmentalized zone, and sequentially labeled with each increasing zone number.
  • a core-sheath design has a minimum of two compartmentalized zones.
  • the core sheath design could have more zones depending upon the number of concentric rings.
  • the size of the compartmentalized zone distinguishes it from a zone associated with a homogenous dispersion.
  • the homogenous dispersion creates zones, but they are finely divided with each zone representing a very small percentage of the total volume of the pellet.
  • the compartmentalized zone will be a much greater percentage of the total volume.
  • the volume of the zone must be at least 0.001 percent of the total volume of the pellet. In practicality, 0.01 volume percent is more preferred, with at least 0.1 volume percent the most preferred.
  • the percentage of the volume of the compartmentalized zone (core) relative to the whole pellet is the ratio of the radius of the core squared to the radius of the cylindrical portion of the pellet squared.
  • a preferred embodiment is the core-sheath design wherein the core comprises m-xylylene adipamide polyamide (MXD6) with a number average molecular weight between 4000 and 50,000 and triamine content after hydrolysis less 0.20 and the sheath comprises a polyester, specifically crystallizable polyethylene terephthalate with an Intrinsic Viscosity (I.V.) between 0.4 and 1.2 dl/g.
  • the phrase crystallizable polyethylene terephthalate, crystallizable polyethylene terephthalates both refer to the group of crystallizable polyesters that have at least 85% of the acid moieties derived from terephthalic acid or the dimethyl ester of terephthalic acid or their equivalents.
  • a polyester made by reacting ethylene glycol with 2 mole percent isophthalic acid and 98 mole percent terephthalic acid is a crystallizable polyethylene terephthalate.
  • both materials can then be further processed under standard conditions of crystallization and solid phase polymerized without generating gels.
  • the article of the invention is indifferent as to whether the materials are crystalline or amorphous.
  • a pellet with a sheath of a 0.49 I.V. amorphous crystallizable polyethylene terephthalate encapsulating a core comprising MXD6 nylon with number average molecular weight 6,000 and a triamine content less than 0.22 prior to crystallization is one of the embodiments of the article. That same pellet after crystallization is one of the embodiments, as is the same pellet which has been solid phase polymerized and the crystallizable polyethylene terephthalate I.V. is 0.84 and the number average molecular weight of the MXD6 nylon has also increased.
  • Another preferred embodiment is to close the ends of the pellet so the inner core 21 is completely surrounded and enclosed by a sheath 21 .
  • One way to make a pellet with an outer layer sheath that encloses the contents of the inner layer(s) is to cut the pellet strand next to the die underwater.
  • the preferred pellet structure is an MXD6 core with triamine content after hydrolysis less than 0.20 surrounded by a polyester copolymer.
  • polyamide zone contain the same crystallizable polyester found in the crystallalizble polyester zone.
  • WO 2005/110694 A1 notes voids may form in the pellet at high strand production speeds and lists specific techniques to reduce voids.
  • the preferred way to eliminate voids is to put the PET ionomer in the polyester. This can be done by using a third PET ionomer or incorporating the ionomeric species, e.g. lithium sulfoisophthalate into the chain of the crystallizable polyester.
  • the polyamides were analyzed for gels by adding 0.1 gm of the thermally treated polyamide to 25 mls of a 1:1 mixture of trifluoroacetic acid (TFA) and CH 2 Cl 2 . Complete dissolution indicated no gels. The presence of gels was indicated by insolubles.
  • TFA trifluoroacetic acid
  • the polyamides were also analyzed for final Relative Viscosity. As is easily seen, the high triamine content had gels, the low triamine content materials did not gel. Those polymers with a large imbalance of end groups did not experience as large an increase in Relative Viscosity as did the polymers with more balanced end groups.
  • Table II demonstrates the utility of these polymers in the compartmentalized pellet.
  • the polyamides with the indicated attributes were placed into the core of a compartmentalized pellet surround by the sheath of a crystallizable polyester. The pellets were then exposed to the solid phase polymerization for the indicated temperature and time. In all cases, the triamine content was high enough to cause gels.
  • the polyamide of the indicated attributes was placed into the core of a compartmentalized pellet, with the sheath of crystallizable polyester. The pellets were then exposed to polyester solid phase polymerization conditions indicated. As can be seen, the polyester increased in I.V. while the polyamide showed no increase in molecular weight as measured by Relative Viscosity or End Group analysis and no gels were evident. It should be noted that the polyesters used in the sheath contained 0.5 mole percent lithium sulfoisophthalic acid. In Experiment 14, possible gels were observed, therefore deserving a rating of “slight”. However, there was no indication of gels in the bottle sidewall, which should have been evident as haze.
  • the intrinsic viscosity of intermediate molecular weight and low crystalline poly(ethylene terephthalate) and related polymers which are soluble in 60/40 phenol/tetrachloroethane can be determined by dissolving 0.1 gms of polymer or ground pellet into 25 ml of 60/40 phenol/tetrachloroethane solution and determining the viscosity of the solution at 30° C. ⁇ 0.05 relative to the solvent at the same temperature using a Ubbelohde IB viscometer. The intrinsic viscosity is calculated using the Billmeyer equation based upon the relative viscosity.
  • the intrinsic viscosity of high molecular weight or highly crystalline poly(ethylene terephthalate) and related polymers which are not soluble in phenol/tetrachloroethane was determined by dissolving 0.1 gms of polymer or ground pellet into 25 ml of 50/50 trifluoroacetic Acid/Dichloromethane and determining the viscosity of the solution at 30° C. ⁇ 0.05 relative to the solvent at the same temperature using a Type OC Ubbelohde viscometer.
  • the intrinsic viscosity is calculated using the Billmeyer equation and converted using a linear regression to obtain results which are consistent with those obtained using 60/40 phenol/tetrachloroethane solvent.
  • the linear regression is
  • the measured density or the required amounts of heat are adjusted by the weighted average of the amount of the compound in the pellet.
  • the amount of each component in the pellet can be determined by many different techniques. For example, one can know how much of the compound was added when manufacturing the pellet, one can physically separate the components, or one can separate the components by dissolving the components away from each other, removing the solvent and taking the weight.
  • formic acid can be used to dissolve the polyamide out of the core, leaving the PET sheath.
  • the amount of PET can be directly weighed and the polyamide amount determined by difference. If the polyamide core contains other compounds which are not soluble in formic acid, the solution can be filtered and the polyamide precipitated from the formic acid by adding water. The sample is then dried and the amount of polyamide determined by direct weighing. In any case, small amounts of additives or other non-polyamide, non-PET materials would not affect the absolute value of the crystallinity to any great extent.
  • the polyamide contains an acid end group and an amino end group.
  • AEG amino end group content
  • CEG carboxylic (or acid) end group content
  • the employed concentrations are defined as amount of end groups (in mol) per mass unit polyamide, for example X mmol end groups per kg polyamide.
  • the conversion to different units of expression is well known in the art. For the purposes of calculating the ratio it is only important that both terms be expressed in the same units.
  • the measurement of the amino end groups can be performed by titration of a solution of the polyamide in presence of an indicator.
  • the polyamide is dissolved by warming a mixture of phenol and methanol (e.g. 75 w. % phenol and 25 w. % methanol).
  • the known amount of polyamide is added to the solution and held until it is dissolved.
  • the mixture can be kept under reflux until a homogeneous solution is obtained.
  • a suitable indicator or indicator mixture e.g. methanolic solution of benzylorange or methylene blue
  • methanolic solution of benzylorange or methylene blue is added to the chilled solution.
  • This mixture is titrated with a methanol containing perchloric acid solution in ethylene glycol, until color changes.
  • the amino end group concentration can be calculated from the consumption of the perchloric acid.
  • the titration can also be performed potentiometrically with a perchloric acid solution in ethylene glycol,
  • This type of analysis is done with a titro-processor (Messrs. Metrohm) as follows. 1 kg phenol is mixed with 429 g of methanol p.a. and slightly warmed. To 50 ml of said solution is added 1 g of polymer granulate and under reverse flow warmed for 20 minutes until the solution reaches 90° C. The solution is titrated with a 0.1 N solution of perchloric acid in ethylene-glycol.
  • the measurement of the carboxylic end groups can also be carried out by titration of a solution of the polyamide by usage of an indicator as well.
  • the polyamide is dissolved in benzyl alcohol (phenylmethanol) by warming, e.g. boiling under nitrogen flush.
  • a suitable indicator or indicator mixture e.g. propanolic solution of cresol red
  • a suitable indicator or indicator mixture e.g. propanolic solution of cresol red
  • This solution is immediately titrated with an alcoholic potassium hydroxide solution (KOH dissolved in a mixture of methanol, 1,-propanol and 1-hexanol), until color changes.
  • KOH alcoholic potassium hydroxide solution
  • the carboxylic end group concentration can be calculated from the consumption of the potassium hydroxide.
  • the titration can also be performed conductrometrically with a NaOH— solution in benzyl alcohol by mixing 1 g of polymer granulate with 50 ml of benzyl alcohol and heated for 30 minutes at 180° C. under reverse flow. A constant stream of nitrogen is passed through. Upon complete dissolution of the polymer, titration is done with 0.1 N of benzyl-alcoholic soda lye.
  • the relative viscosity of the polyamide, including MXD6, was measured with samples of 1 g polyamide in 100 ml 96 w. % sulphuric acid by using a Ubbelohde viscometer 2 Type 50120 (Schott) according to DIN EN ISO 1628-1 and ISO 307-1984.
  • the triamine content after hydrolysis is measured after complete hydrolysis of the polyamide by using capillary electrophoresis combined with UV detection.
  • the quantification is effected by the method of the internal standard, N-methyl-imidazole
  • the polyamide is hydrolyzed by heating 200 mg of the polyamide in 15 ml 1N sulphuric acid in an autoclave at 180° C. for 4 hours. 0.5 ml of the hydrolyzed solution is mixed with 1 ml solution of the internal standard. The sulphate is then precipitated as BaSO 4 by adding cold saturated Ba(OH) 2 until reaching a pH of 6 as measured by a standard pH electrode. The residual solution is diluted with water to a volume of 50 ml.

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