WO1996013539A1 - Polycarbonate and polyester compositions - Google Patents
Polycarbonate and polyester compositions Download PDFInfo
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- WO1996013539A1 WO1996013539A1 PCT/US1995/013869 US9513869W WO9613539A1 WO 1996013539 A1 WO1996013539 A1 WO 1996013539A1 US 9513869 W US9513869 W US 9513869W WO 9613539 A1 WO9613539 A1 WO 9613539A1
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- 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
- C08G63/02—Polyesters derived from hydroxycarboxylic acids or from polycarboxylic acids and polyhydroxy compounds
- C08G63/12—Polyesters derived from hydroxycarboxylic acids or from polycarboxylic acids and polyhydroxy compounds derived from polycarboxylic acids and polyhydroxy compounds
- C08G63/52—Polycarboxylic acids or polyhydroxy compounds in which at least one of the two components contains aliphatic unsaturation
- C08G63/54—Polycarboxylic acids or polyhydroxy compounds in which at least one of the two components contains aliphatic unsaturation the acids or hydroxy compounds containing carbocyclic rings
- C08G63/547—Hydroxy compounds containing aromatic rings
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- 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
- C08G63/02—Polyesters derived from hydroxycarboxylic acids or from polycarboxylic acids and polyhydroxy compounds
-
- 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
- C08G63/64—Polyesters containing both carboxylic ester groups and carbonate groups
-
- 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
- C08G64/00—Macromolecular compounds obtained by reactions forming a carbonic ester link in the main chain of the macromolecule
- C08G64/04—Aromatic polycarbonates
- C08G64/045—Aromatic polycarbonates containing aliphatic unsaturation
Definitions
- This invention relates to polycarbonates, polyesters, and polyestercarbonates prepared from at least one aromatic diol, wherein a portion or all of the aromatic diol used in their preparation is a stilbene diol.
- 2613 (1988) reports the synthesis of mixed aromatic-aliphatic polyesters using 4,4'-dihydroxy-alpha,alpha'-diethylstilbene and adipoyl chloride, sebacoyl chloride, and mixtures of adipoyl and sebacoyl chlorides.
- the physical properties and melt characteristics of such polymers may be less than desirable for certain applications.
- this invention is a polycarbonate, polyester, or polyestercarbonate composition prepared from a reaction mixture comprising at least one diol and at least one carbonate precursor or ester precursor, wherein
- dialkyl carbonates diarylcarbonates, carbonyl halides, or bis(trihlaoalkyl) carbonates
- aromatic dicarboxylic acids hydroxybenzoic acids, hydroxynapthoic acids, hydroxybiphenyl acids, hydroxycinnamic acids, or the halides or metal salts of such acids; or (iii) oligomers and polymers of (i) or (ii) containing carbonate or ester groups, which are prepared by contacting an excess over stoichiometry of at least one compound selected from (i) or (ii) with at least one monol or diol under reaction conditions sufficient to form the corresponding oligomer or polymer; or (b) at least 95 mole percent of the diol present in the reaction mixture consists of one or more aromatic diols, at least 10 mole percent of which consists of one or more stilbene diols.
- composition of the invention has an advantageous thermal resistance, melting temperature, tensile and flexural properties, and/or resistance to thermal embrittlement.
- those polymers of the invention which are thermotropic liquid crystalline also have an advantageous temperature range for liquid crystallinity, melt processibility, coefficient of thermal expansion, ignition resistance, solvent resistance, and/or barrier properties.
- the polymeric composition of the invention may be prepared by any method suitable for the preparation of polycarbonate, polyester, or polyestercarbonate polymers, so long as at least 95 mole percent of the diol present in the polymerization reaction mixture consists of one or more aromatic diols, and at least 10 mole percent of the aromatic diols 5 consists of one or more stilbene diols. Such methods include interf acial, solution, and melt polymerization processes. Further, the polymeric composition of the invention may be prepared as a homopolymer, or as a random or block copolymer of the various monomers described below.
- reaction mixture refers to the mixture of monomers which are polymerized to form the composition of the invention, utilizing any of o the polymerization methods described in any of the references cited herein.
- composition of the invention preferably comprises repeating units of the formulas:
- R independently in each occurrence is the divalent nucleus of an aromatic diol
- X is selected from: -C(O)-, -CfO -R'-CfO)-, or a mixture thereof
- R 1 independently in each occurrence is the divalent nucleus of a difunctional aromatic carboxylic acid
- R 2 is the divalent nucleus of an aromatic hydroxy carboxylic acid.
- other monomers 0 such as hydroxy carboxylic acids may also be present in the polymerization reaction mixture, in addition to the diols and carbonate precursors.
- divalent nucleus refers to the compound described, minus its pendant hydroxyl and/or carboxyl groups.
- the polymeric composition of the invention is a polycarbonate
- it may be prepared by the reaction of an aromatic diol or mixtures of aromatic diols with a carbonate 5 precursor.
- carbonate precursor refers to carbonyl halides, diaryl carbonates, dialkyl carbonates, bis(trihaloalkyl)-carbonates such as triphosgene, bishaloformates, and other compounds which will react with hydroxyl groups to form carbonate linkages (-O-C(O)-O-).
- suitable carbonyl halides include carbonyl bromide, carbonyl chloride (“phosgene") and mixtures thereof.
- Suitable haloformates include the bischloroformates of dihydric phenols such as bisphenol A.
- the carbonate precursor is phosgene or diphenyl carbonate, and is most preferably diphenyl carbonate. Examples of suitable methods for preparing polycarbonates are set forth in "Polycarbonates,” Encyclopedia of Polymer Science and Enqineerinq (2nd Edition). Vol. 11, pp. 648-718 (1988); U.S. Patent Nos.
- the polymeric composition of the invention when the polymeric composition of the invention is a polyester, it may be prepared by the reaction of an aromatic diol or a reactive derivative thereof (such as the corresponding diacetate), with an ester precursor
- ester precursor refers to Cg- o dicarboxylic acids or reactive derivatives thereof (such as esters thereof or the corresponding acid halides), which will react with hydroxyl groups to form ester linkages (-0-C(0)-R 1 -C(0)-0-, wherein R 1 is the divalent nucleus of the ester precursor).
- the ester precursor is an aromatic dicarboxylic acid.
- ester component in these polymeric compositions may optionally be derived from hydroxycarboxylic acids or reactive derivatives thereof, either by reaction with the other monomers or self-condensation, to provide repeat units of Formula (II): -[R 2 -C(0)-0]-, wherein R 2 is the divalent nucleus of a hydroxycarboxylic acid.
- suitable methods for preparing polyesters are set forth in "Polyesters,” Encyclopedia of Polymer Science and Enqineerinq (2nd Edition), Vol. 12, pp. 1-75 (1988); “Liquid Crystalline Polymers,” Encyclopedia of Polymer Science and Enqineerinq (2nd Edition), Vol. 9, pp.
- the polymeric composition of the invention when it is a polyestercarbonate, it may be prepared by the reaction of an aromatic diol with a combination of a carbonate precursor and an ester precursor as described above. Suitable methods for the preparation of polyestercarbonates are described in U.S.
- oligomers and polymers of (i) or (ii) containing carbonate or ester groups which are prepared by contacting an excess over stoichiometry of at least one compound selected from (i) or (ii) with at least one monol or diol under reaction conditions sufficient to form the corresponding oligomer or polymer.
- oligomer as used herein includes monoesters, diesters, monocarbonates, and dicarbonates of the monol or diol.
- Suitable stilbene diols for use in the preparation of the polymeric composition of the invention include those of the formula:
- R 3 independently in each occurrence is selected from hydrogen, C alkyl, chlorine, bromine, or cyano, but is preferably hydrogen or C alkyl
- R 4 independently in each occurrence is selected from hydrogen, halogen, alkyl, aryl, alkoxy, aryloxy, cyano, nitro, carboxamide, carboximide, or R 5 -C(0)-, wherein R 5 is C. ⁇ alkyl or aryloxy, but is preferably hydrogen or C alkyl.
- the phenolic groups are in a "trans" configuration the double bond.
- the stilbene diol is 4,4'-dihydroxystilbene; 4,4'-dihydroxy-alpha-methy!stilbene; 4,4'-dihydroxy-alpha,alpha'-dimethylstilbene; or4,4'-dihydroxy-alpha,alpha'-diethylstilbene.
- the stilbene diols described above may be prepared by any suitable method.
- the diol is prepared from a phenol and a carbonyl-containing precursor, using any of the procedures described by S. M. Zaher et al., Part 3, J. Chem. Soc, pp. 3360-3362 (1954); V. Percec et al., Mol. Cryst. Liq. Cryst, Vol.
- color bodies, or color forming bodies may be removed from the stilbene diols by contacting them with an aqueous solution of one or more compounds selected from alkali metal carbonates, alkali earth metal carbonates, alkali metal bicarbonates (such as sodium bicarbonate), or alkaline earth metal carbonates.
- the stilbene diol(s) used to prepare the composition of the invention preferably have a 4,4'-isomeric purity of at least 95 mole percent, more preferably at least 98 mole percent and most preferably at least 99 mole percent.
- one or more additional aromatic diols may also be used to prepare the composition of the invention. Suitable aromatic diols include any aromatic diol which will react with a carbonate precursor or ester precursor.
- Preferred diols include 2,2-bis(4-hydroxyphenyl)propane ("bisphenol A”); 9,9-bis(4-hydroxyphenyl)f luorene; hydroquinone; resorcinol; 4,4'-dihydroxybiphenyl; 4,4'-thiodiphenol; 4,4'-oxydiphenol; 4,4'-sulfonyldiphenol; 4,4'-dihydroxybenzophenone; 4,4"-dihydroxyterphenyl; 1,4-dihydroxynaphthalene; 1,5-dihydroxynaphthalene; 2,6-dihydroxynaphthalene; bis(4-hydroxyphenyl)methane ("bisphenol F”); and inertly substituted derivatives thereof , as well as mixtures thereof.
- the diol is 2,2-bis(4-hydroxyphenyl)propane ("bisphenol A").
- At least 95 mole percent of the diols present in the reaction mixture consist of one or more aromatic diols.
- at least 98 mole percent, and more preferably 100 mole percent of such diols are aromatic diols.
- at least 10 mole percent of the aromatic diol present in the reaction mixture consists of one or more stilbene diols.
- at least 25 mole percent, and more preferably at least 50 mole percent of such aromatic diols are stilbene diols.
- aromatic dicarboxylic acids which may be used to prepare polyester or polyestercarbonate compositions of the invention include terephthalic acid; isophthalic acid; 2,6-naphthalenedicarboxylic acid; 1,4-naphthalenedicarboxylic acid; 1,5-naphthalene- -dicarboxylic acid; 4,4'-biphenyldicarboxylic acid; 3,4'-biphenyldicarboxylic acid; 4,4'-terphenyldicarboxylic acid; 4,4'-stilbenedicarboxylic acid; 4,4'-dicarboxy-alpha- -methylstilbene; inertly substituted derivatives thereof, as well as mixtures thereof.
- hydroxycarboxylic acids examples include 4-hydroxybenzoic acid; 3-hydroxybenzoic acid; 6-hydroxy-2-naphthoic acid; 7-hydroxy-2- -naphthoic acid; 5-hydroxy-1-naphthoic acid; 4-hydroxy-1-naphthoic acid; 4-hydroxy-4'- -biphenylcarboxyli acid; 4-hydroxy-4'-carboxydiphenyl ether; 4-hydroxycinnamic acid; inertly substituted derivatives thereof, as well as mixtures thereof.
- Chain stopping agents are monof unctional compounds which react with a carbonate or ester precursor site on the end of the polymer chain and stop the propagation of the polymer chain.
- suitable chain stopping agents include monofunctional aromatic alcohols, thiols, and amines, as well as mixtures thereof.
- the chain stopping agent is a monofunctional aromatic alcohol, thiol, amine, aliphatic alcohol, aromatic carboxylic acid, aliphatic carboxylic acid, or a mixture thereof.
- the compositions of the present invention are preferably of the following formula:
- F and G are, independently, either hydrogen or other terminating groups common to polycarbonates, polyesters carbonates, or polyesters.
- F and G are o represented by the formulas:
- the polymers of the present invention preferably have a weight average 5 molecular weight (Mw, determined by size exclusion chromatography using a bisphenol A polycarbonate calibration curve) of at least 10,000, more preferably at least 20,000.
- Preferred polymers according to the present invention have inherent viscosities, measured in methylene chloride (for an amorphous polymer) at 0.5 grams per deciliter (g/dL) and 25°C, or in pentafluorophenol (for a crystalline or liquid crystalline polymer) at 0.1 g/dL and 45°C, of at 0 least 0.2 dL/g and more preferably at least 0.35 dL/g.
- Liquid crystalline polymeric compositions may be identified using one or more standard techniques, such as heating the composition on a differential scanning calorimeter and characterizing it in the melt state by optical microscopy under cross-polarized light. Thermotropic liquid crystalline polymers will exhibit optical anisotropy upon melting. Other 5 techniques which may be used to characterize the polymer as liquid crystalline include scanning electron microscopy, X-ray diffraction, visible light scattering techniques, electron beam diffraction, infrared spectroscopy, and nuclear magnetic resonance. If the composition is liquid crystalline, it preferably has nematic ordering in the liquid crystalline melt state.
- the compositions of the invention advantageously have a 0 relatively high thermal resistance, melting temperature, tensile and flexural properties, and/or resistance to thermal embrittlement.
- those polymers of the invention which are thermotropic liquid crystalline also advantageously possess a broad temperature range for liquid crystallinity, good melt processibility, a low coefficient of thermal expansion, a high ignition resistance, high solvent resistance, and/or good barrier properties.
- the thermal 5 resistance of the composition may be characterized by its Vicat softening temperature and the temperature at which it may be distorted under load, as illustrated in Example 2.
- the tensile and flexural properties of the composition may be characterized and measured in accordance with ASTM D-638, as illustrated in the examples.
- the composition's resistance to thermal embrittlement refers to its tendency to become brittle at elevated temperature, and may be characterized by measurement of its post yield stress drop, as illustrated in Example 7.
- the composition of the invention when thermotropic liquid crystalline, also preferably has thermal characteristics which permit it to be readily processed in the liquid crystal state when heated above its melt temperature.
- the temperature range over which such polymers may be processed above their melt temperature in the liquid crystal state is preferably as broad as possible, but is preferably at least 25°C, more preferably at least 50 C C, and is most preferably at least 100°C In most instances, the composition will become isotropic above this range, in which case the range may be expressed as the difference between the clearing o temperature (T c
- the clearing temperature is the temperature at which the composition undergoes a transition from the anisotropic liquid crystalline state to an isotropic state (see, for example, The Encyclopedia of Polymer Science and Enqineerinq, Vol. 9, p. 55 (1988).
- the melt processibility of the polymeric composition may be characterized by its 5 melt temperature and its melt viscosity, as illustrated in the examples.
- the melt temperature of the composition (T m , as determined by Differential Scanning Calorimetry) when thermotropic liquid crystalline, is preferably at least 200°C, more preferably at least 250°C, but is preferably no greater than 350°C.
- the coefficient of thermal expansion of the composition of the invention may be 0 measured in accordance with ASTM D-2236, as illustrated in the Examples below.
- the ignition resistance of the polymers may be measured by determining the Limiting Oxygen Index of the composition, by testing the composition in accordance with Underwriters Laboratories' test number UL-94, or by measuring the char yield of the composition by thermal gravimetric analysis.
- the solvent resistance of the composition of the invention may be characterized as 5 shown in the examples.
- the barrier properties of the composition of the invention may be measured in accordance with ASTM D-3985 (oxygen transmission rate) and ASTM F-372 (carbon dioxide and water vapor transmission rate).
- composition of the invention may be subjected to post-condensation in the solid phase (also known as solid-state advancement), preferably under reduced pressure, at a temperature in the range from 150°C to 350°C. After 1 to 24 hours, the molecular weight has increased and the resulting polymers exhibit further improved properties.
- the composition of the present invention may be fabricated using any of the known thermoplastic molding procedures, including compression molding, injection molding, and extrusion to provide fabricated articles, including moldings, boards, sheets, tubes, fibers, and films. Procedures that may be employed to maximize the orientation of the liquid crystal moieties contained in fabricated articles from the polymers of the invention are summarized in U.S. Patent No. 5,300,594, as well as the references cited therein.
- composition of the present invention can also be employed with other thermoplastic polymers to prepare thermoplastic polymer blends.
- Suitable thermoplastics for this purpose include polycarbonates, polyesters, polyethers, polyetherketones, polysulf ides, polysulfones, polyamides, polyurethanes, polyimides, polyalkylenes such as polyethylenes and polypropylenes, polystyrenes, copolymers thereof and mixtures thereof.
- the polymers of this invention may, in addition to being used for molding purposes, be employed as the base for preparing thermoplastic molding compositions by being compounded with antioxidants, antistatic agents, inert fillers and reinforcing agents such as glass fibers, carbon fibers, talc, mica, and clay, hydrolytic stabilizers, colorants, thermal stabilizers, flame retardants, mold o release agents, plasticizers, UV radiation absorbers, and nucleating agents as described in U.S. Patent Nos. 4,945,150 and 5,045,610 and the other references cited above.
- Example 1 Preparation of Polycarbonate of 4,4'-Dihydroxy-alpha-methylstilbene (DHAMS) The polymerization was run in a 1 L single-neck round-bottom flask fitted with a two-neck adapter upon which were mounted a glass paddle stirrer and a 13 centimeter (cm) Vigreaux distillation column, distillation head with a thermometer, condenser and a receiver. DHAMS (1.79 mol, 403.6 g) and diphenylcarbonate (1.93 mol, 412.7 g) were added to the 0 reaction flask. The.
- the apparatus was evacuated and refilled with nitrogen three times.
- the flask was immersed in a molten salt bath preheated to 220°C.
- stirring was started and an aqueous solution of lithium hydroxide (0.82 mL, 0.06 M) was added as a catalyst.
- the reaction temperature was raised to 290°C over a period of 1 hour and the pressure was reduced from atmospheric pressure to 5 2x10 "3 atmospheres. The latter pressure was maintained for one hour at 290°C. After an additional 5 minutes the reaction mass formed a ball on the stirrer shaft.
- the vacuum was then released under nitrogen and the reaction vessel was removed from the salt bath.
- the reaction apparatus was cooled and disassembled.
- the distillation receiver contained 337 g of phenol.
- the flask was broken away from the opaque chalk-white polycarbonate plug.
- the plug was 0 sawed into chunks and then ground in a Wiley mill.
- the product was dried in a vacuum oven at 100°C for 2 hours to give 408 g of product (91 percent yield).
- the polycarbonate had an inherent viscosity (IV) of 2.6 dL/g, measured at 45°C using a solution of 0.1 g of polycarbonate in 100 mL of pentaf luorophenol.
- DSC Differential scanning calorimetry
- 5 showed a peak melting point of 273°C (first heating scan, run from 25°C to 320°C) and a crystallization temperature of 202°C (first cooling scan, run from 320°C to 50°C).
- a second heating scan showed a peak endotherm at 272°C, and a second cooling scan showed a crystallization temperature at 194°C.
- the apparatus used for determining optical anisotropy included a THM 600 hot stage (Linkham Scientific Instruments LTD, Surrey, England) and a Nikon Optiphot Microscope equipped with crossed-polarizers and a 35 mm camera (Nikon Instrument Group, Nikon, Inc., Garden City, N.Y). Observation of a bright field at temperatures above the melting point indicated that the DHAMS polycarbonate melt was optically anisotropic.
- the sample was placed on the programmable hot stage and a heating rate of 50°C/minute was used initially from 25°C to 180°C, then 10°C/minute was used from 180°C to 250°C and then 5°C/minute was used from 250°C to 300°C.
- thermotropic liquid crystalline DHAMS polycarbonate prepared in this example was insoluble in conventional organic solvents both at room temperature and 5 elevated temperatures. Solvents that do not dissolve this polycarbonate include methylene chloride, chloroform, carbon tetrachloride, tetrahydrof uran, acetone, N,N-dimethylacetamide, dimethylsulf oxide, pyridine, and trifluoroacetic acid/methylene chloride (4/1 volume ratio).
- the polycarbonate was soluble in pentafluorophenol at high dilutions (0.1 g/dL). Melt Viscosity Determination 0 The melt viscosity of the DHAMS polycarbonate sample was determined using an
- Instron 3211 capillary rheometer with capillary length of 1.0087 inch, capillary diameter of 0.05005 inch, a shear rate range of 3.5 to 350 sec ', and a temperature of 290°C.
- the samples for the rheometer were prepared by placing a pre-dried, (100°C vacuum oven dried) polymer sample (1 g) in a stainless steel die, pressing in a hydraulic press at a platen pressure of 3,000 5 pounds for a few minutes and obtaining cylindrical pellets.
- the melt viscosity of DHAMS polycarbonate was determined to be 810 poise at 100 sec '1 and 250 poise at 400 sec '1 .
- TGA is run using a Du Pont 2100 thermal analyzer, a temperature scan range from 25°C to 1000°C, a heating rate of 10°C/minute, and a nitrogen purge.
- the residue remaining at 0 1000 C C also known as the char yield, is 38 percent for DHAMS polycarbonate.
- the significance of char yield and its relation to ignition resistance were discussed by Van Krevelen, Properties of Polymers, p. 731 (Third Edition, 1990).
- DHAMS polycarbonate prepared according to the procedure of Example 1, was 5 ground in a Thomas-Wiley model 4 laboratory mill, dried at 100°C in a vacuum oven for 2 hours, and then injection molded using an Arburg injection molding machine. Standard 0.125 inch thick test specimens were injection molded at a barrel temperature of 300°C, a mold temperature of 125°C, and using 275 bars of injection pressure.
- Tensile strength at break (Tb), tensile modulus (TM), elongation at break (Eb), flexural strength (FS), and flexural modulus (FM) were determined according to American Society for Testing and Materials (ASTM) test method D-638.
- the notched Izod impact strength was determined according to ASTM D-256 wherein a 0.01 inch notch radius was employed.
- Vicat softening temperature for the polymer was determined according to ASTM D-1525 using a 1 kg load.
- the coefficient of linear thermal expansion (CLTE) in the flow direction was measured according to ASTM D-2236.
- Limiting oxygen index (LOI) was determined according to ASTM D-2863-87.
- UL-94 determinations of flammability resistance was conducted as specified by Underwriters Laboratories. Water absorption was measured at 25 C C after 24 hours immersion time. Specific gravity was measured according to ASTM D-570.
- Example 4 Preparation of Mixture of DHAMS Polycarbonate and Glass Fibers DHAMS polycarbonate (prepared as in Example 1) (417 g) was dry mixed with
- DHAMS polycarbonate with an IV of 1.5 dL/g (measured in pentaf luorphenol at 0.1 g/dL and 45°C) and BA polycarbonate with a Condition O melt flow rate of 10 g/10 minutes were each separately cryogenically ground to a fine powder.
- a portion (0.5011 g) of the DHAMS polycarbonate and a portion (4.50 g) of the BA polycarbonate were combined and mixed.
- the resulting mixture (4.76 g) was added over an 8 minute period to the stirred reservoir of an injection molder which was preheated to 260°C After addition of the mixture was completed, the stirred mixture was maintained for an additional 12 minutes at the 260°C temperature prior to shutting off the stirring.
- the mixture was then injected into a 3 inch by 0.5 inch by 0.125 inch stainless steel mold which was preheated to 260°C.
- the copolymerization was run in a 250 mL, single-neck, round-bottom flask, fitted with a two-neck adapter upon which were mounted a glass paddle stirrer and a 13 centimeter (cm) Vigreaux distillation column, distillation head with a thermometer, condenser and a receiver.
- DHAMS (0.11 moles, 24.19 grams)
- BA 0.012 moles, 2.71 grams
- diphenylcarbonate (0.12 moles, 25.46 grams
- the copolycarbonate had an inherent viscosity of 0.91 dL/g which was measured at 45°C using a solution of 0.1 g of polycarbonate in 100 mL of pentafluorophenol.
- the peak melting point was 250 C C on the first heating scan as measured by differential scanning calorimetry (DSC) on a sample run at 10°C/minute.
- a second heating scan showed only a T g at 84°C and no melting point transition is observed.
- copolycarbonate was characterized by optical microscopy under cross- -polarized light. Observation of a bright field at temperatures above the melting point indicated that the copolycarbonate melt was optically anisotropic.
- copolycarbonates of DHAMS and BA were prepared according to the general procedure described above. These copolycarbonates were based on DHAMS/BA molar ratios of 90/10 to 50/50. The copolycarbonates were characterized by DSC for the determination of glass transition temperature (T g ) and melting temperature (Tm), IV, TGA
- DHAMS/BA 50/50 molar ratio copolycarbonate
- a 2 L four-neck, round-bottom flask, equipped with a thermometer, condenser, phosgene/nitrogen inlet, and a paddle stirrer connected to a Cole Parmer servodyne was charged with DHAMS (26.80 g, 0.118 mol), BA (27.04 g, 0.118 mol), 4-tertbutylphenol (0.71 g, 4.7 mmol, a chain terminator), pyridine (48.5 g, 0.614 mol), and methylene chloride (0.5 L).
- the mixture was stirred at 250 rpm and slowly purged with nitrogen as phosgene (24.8 g, 0.251 mol) was bubbled in over 28 minutes while maintaining the reactor temperature at 17°C to 26 D C.
- the reaction mixture was worked up by adding methanol (5 mL) and then a solution of 20 mL cone. HCI in 60 mL water. After stirring for 15 minutes at 200 rpm, the mixture was poured into a 2 L separatory funnel. The methylene chloride layer was separated and washed further with a solution of 5 mL conc. HCI in 100 mL water, followed by 100 mL water, and then passed through a column (0.2 L bed volume) of macroporous cation-exchange resin.
- the product was isolated by adding the clear methylene chloride solution to a mixture of hexane (2 L) and acetone (0.2L) in an explosion resistant blender. The product was filtered, dried in a hood overnight, and then dried for 48 hours in a vacuum oven at 110°C. The dried product weighed 55.6 g and had an IV of 0.846 dL/g (determined in methylene chloride at 0.5 g/dL and 25°C). DSC analysis (first scan, 20°C/minute heating rate, scan from 50°C to 250°C) showed an extrapolated onset glass transition temperature (T ) of 144°C. The second scan showeds a T g at 141°C.
- Compression molded plaques of approximately 6 inch x 6 inch x 0.125 inch were prepared at molding temperatures 100 C C above T g using a Tetrahedron MTP-14 press. These transparent plaques were machined into test specimens.
- Tensile strength at yield (Ty), elongation at yield (Ey), and post-yield stress drop (PYSD) are determined according to ASTM D-638. A reduction in PYSD had been correlated with enhanced resistance to physical aging and fatigue, resulting in improved long-term property maintenance: see R. Bubeck et al., Polym. Eng. Sci., Vol. 24, p. 1142 (1984). IV, T g , and notched Izod were determined as described above. These results are shown in Table II.
- Example 7 The same equipment as described in Example 7 was charged with DHAMS (40.30 g, 0.178 mol), BA (13.55 g, 0.059 mol), 4-tertbutylphenol (0.71 g, 4.7 mmol), pyridine (48.7 g, 0.616 mol), and methylene chloride (0.5 L). The mixture was stirred at 250 rpm and slowly purged with nitrogen as phosgene (24.4 g, 0.247 mol) was bubbled in over 21 minutes while maintaining the reactor temperature at 18°C to 26 C C. The product began to precipitate from the reaction solution when 13 g of phosgene was added. The same workup procedure as shown in Example 7 was followed, except that the product was not passed through a column of ion exchange resin. For this composition the product was a slurry in methylene chloride rather than a solution.
- phosgene 24.4 g, 0.247 mol
- the product was isolated by adding the slurry to 3 L of methanol in an explosion resistant blender. The product was filtered, dried in a hood overnight, and then dried for 48 hours in a vacuum oven at 110°C. The product weighed 59.6 g and was insoluble in the following solvents that dissolve BA polycarbonate: methylene chloride, chloroform, tetrahydrofuran, dimethylformamide, and sym-tetrachloroethane.
- a compression molded plaque (approximately 0.02 inch thickness) prepared at 250°C (3 minutes molding time, 10,000 o pounds platen pressure) was well-fused, opaque, creasable, insoluble in the solvents listed above, and does not stress crack when flexed and exposed to acetone.
- Example 10 Preparation of Polyestercarbonate from DHAMS, Diphenyl Terephthalate, and Diphenyl Carbonate
- the polymerization was run in a 250 mL single-neck, round-bottom flask, fitted with a two-neck adapter upon which are mounted a glass paddle stirrer and a 13 cm Vigreaux distillation column, distillation head with a thermometer, condenser and a receiver.
- Diphenyl terephthalate (0.0143 mol, 3.64 g, an ester derivative of terephthalic acid), DHAMS (0.11 mol, 25.84 g), and diphenyl carbonate (0.10 mol, 22.02 g) was added to the reaction flask.
- the apparatus was evacuated and refilled with nitrogen three times.
- the flask was immersed in a molten salt bath preheated to 220°C. When the solid reactants had melted to form a molten reaction mass, stirring was started and lithium hydroxide (0.36 mL of 0.06 M aqueous solution) was added.
- the reaction temperature was raised to 265 C C over a period of one hour and the pressure was reduced from atmospheric pressure to 2x10 '3 atmospheres. The latter pressure was maintained for 1 hour at 265°C After an additional 5 minutes the reaction mass formed a ball on the stirrer shaft. The vacuum was then released under nitrogen and the reaction vessel was removed from the salt bath. The reaction apparatus was cooled and disassembled. The volume of phenol recovered was 20.1 mL The flask was broken away from an opaque chalk- white product. The plug was sawed into chunks and then ground in a Wiley mill. The polyestercarbonate had an inherent viscosity of 1.05 dL/g (pentafluorphenol, 45 C C, 0.1 g/dL).
- the polymerization was run in a 250 mL single-neck, round-bottom flask, fitted with a two-neck adapter upon which were mounted a glass paddle stirrer and a 13 cm Vigreaux distillation column, distillation head with a thermometer, condenser and a receiver.
- Terephthalic acid 0.084 mol, 13.99 g
- DAAMS 0.084 mol, 26.12 g
- the apparatus was evacuated and refilled with nitrogen three times.
- the flask was then immersed in a molten salt bath preheated to 260 C C.
- the white suspension became a slurry over the next 2 hours as the temperature was slowly raised to 360°C.
- the pressure was slowly lowered to 2x10 '3 atmospheres. After an additional 30 minutes, the apparatus was cooled, and the vacuum was released under nitrogen. The isolated amount of opaque, pale yellow polyester was 26 g.
- the receiver contained 9.7 mL of acetic acid.
- the polyester was ground to a powder and was found to be insoluble in pentaf lurophenol at 0.1 g/dL and 45°C. DSC analysis of the polymer resulted in no observable endotherms or exotherms in the analysis range of 25°C to 400°C.
- Example 12 Preparation of Copolyester f rom DAAMS, Isophthalic Acid, 4-AcetoxybenzoicAcid (ABA), and 2,6-Naphthalenedicarboxylic Acid (NDCA)
- the polymerization was run in a 250 mL single-neck, round-bottom flask, fitted with a two-neck adapter upon which were mounted a glass paddle stirrer and a 13 cm Vigreaux distillation column, distillation head with a thermometer, condenser and a receiver.
- ABA (0.102 mol, 18.232 g), isophthalic acid (0.0169 mol, 2.80 g), NDCA (0.017 mol, 3.65 g), and DAAMS (0.034 mol, 10.46 g) were added to the reaction flask.
- the apparatus was evacuated and refilled with nitrogen three times.
- the flask was immersed in a molten salt bath preheated to 260°C.
- stirring was started and lithium hydroxide (0.36 mL of 0.06 M aqueous solution) was added.
- the reaction temperature was raised to 340 C C over a period of 2 hours at atmospheric pressure.
- This polycarbonate was prepared according to the general procedure of Example 1 using DES (0.14 mol, 36.5 g) and diphenyl carbonate (0.15 mol, 32.1 g). During the synthesis, conducted from 220 to 290°C, the reaction mixture remained isotropic. Phenol (25 g) was removed as a distillate during the synthesis. The isolated yield of DES polycarbonate is 37 g. This polycarbonate had an IV of 0.37 dL/g (determined in chloroform at 25°C). DSC analysis showed a T g at 87°C and no indications of a melting transition in the scan range of 25°C to 300°C. The polycarbonate was annealed at 125°C for 12 hours under an atmosphere of nitrogen. DSC analysis of the annealed sample showed a T g at 92°C, but no evidence of melting transitions.
- This copolycarbonate was prepared according to the general procedure of Example 1 using DES (0.016 mol, 4.19 g), DHAMS (0.14 mol, 31.76 g), and diphenyl carbonate (0.16 mol, 33.41 g). During the synthesis, conducted from 220°C to 290°C, the reaction changed from an isotropic liquid to an opaque molten state at 270°C. Phenol (29 g) was removed as distillate during the synthesis. The resulting copolycarbonate was obtained as a white crystalline solid in an isolated yield of 35 g.
- DSC analysis showed a T g at 87°C and a melting transition at 237°C during the heating scan and a crystallization exotherm at 112°C during the cooling scan.
- the polymer was insoluble in methylene chloride and chloroform at 0.1 g/dL.
- the polymer melt was optically anisotropic as determined by optical microscopy analysis described above.
- Example 15 Preparation of DHAMS/4,4'-Dihydroxystilbene (DHS) Copolycarbonate
- DHAMS/DHS (90/10 molar ratio) copolycarbonate was prepared according to the general procedure of Example 1 using DHS (0.02 mol, 3.35 g), DHAMS (0.14 mol, 32.5 g), and diphenyl carbonate (0.16 mol, 34.2 g).
- DHS was prepared according to the procedure of McMurry and Silvestri, J. Orq. Chem.. Vol.40, p. 2687 (1975). The polymerization was conducted from 220°C to 290°C. The reaction mixture beame opaque at 280°C.
- This copolycarbonate was prepared according to the general procedure of Example 1 using DHS (0.04 mol, 8.45 g), DHAMS (0.121 mol, 27.3 g), and diphenyl carbonate (0.16 mol, 34.5 g). The reaction was conducted from 220°C to 320 C C and the reaction mixture became opaque at 285°C. Phenol (30 g) was removed as a distillate during the synthesis. The resulting copolycarbonate, 35 g, was isolated as a white fibrous solid. The polymer was insoluble in methylene chloride or chloroform at 0.1 g/dL DSC analysis showed a sharp melting transition at 299°C and a crystallization exotherm at 228°C. The melt was optically anisotropic as determined by the methods described above.
Abstract
Description
Claims
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP95938924A EP0789722A1 (en) | 1994-10-31 | 1995-10-27 | Polycarbonate and polyester compositions |
KR1019970702782A KR970707207A (en) | 1994-10-31 | 1995-10-27 | Polycarbonate and polyester compositions (Polycarbonate and plyester compositions) |
JP8514736A JPH10508064A (en) | 1994-10-31 | 1995-10-27 | Polycarbonate and polyester compositions |
CA 2202979 CA2202979A1 (en) | 1994-10-31 | 1995-10-27 | Polycarbonate and polyester compositions |
FI971834A FI971834A (en) | 1994-10-31 | 1997-04-29 | Polycarbonate and polyester compositions |
MXPA/A/1997/003223A MXPA97003223A (en) | 1994-10-31 | 1997-04-30 | Polycarbonate and polyes compositions |
Applications Claiming Priority (4)
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US33177994A | 1994-10-31 | 1994-10-31 | |
US08/542,489 | 1995-10-13 | ||
US08/331,779 | 1995-10-13 | ||
US08/542,489 US5614599A (en) | 1994-10-31 | 1995-10-13 | Stilbene-based polyester and polycarbonate compositions |
Publications (1)
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WO1996013539A1 true WO1996013539A1 (en) | 1996-05-09 |
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PCT/US1995/013869 WO1996013539A1 (en) | 1994-10-31 | 1995-10-27 | Polycarbonate and polyester compositions |
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US (1) | US5614599A (en) |
EP (1) | EP0789722A1 (en) |
JP (1) | JPH10508064A (en) |
KR (1) | KR970707207A (en) |
FI (1) | FI971834A (en) |
WO (1) | WO1996013539A1 (en) |
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EP2243797A1 (en) * | 2008-03-27 | 2010-10-27 | Terumo Kabushiki Kaisha | Bioabsorbable material and device using the same to be placed in the living body |
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US5854375A (en) * | 1997-01-15 | 1998-12-29 | The Dow Chemical Company | Melt polymerization process for preparing aromatic polyesters |
US7105627B1 (en) * | 2005-08-15 | 2006-09-12 | General Electric Company | Polyester stilbene composition |
US20070037960A1 (en) * | 2005-08-15 | 2007-02-15 | General Electric Company | Copolyester stilbene embossed film and methods of making the same |
JP5197062B2 (en) * | 2008-02-20 | 2013-05-15 | 日東電工株式会社 | Birefringent film and polarizing element |
JP5383299B2 (en) * | 2009-04-16 | 2014-01-08 | 日東電工株式会社 | Optical film and manufacturing method thereof |
JP2011065142A (en) * | 2009-08-15 | 2011-03-31 | Nitto Denko Corp | Liquid crystal panel and liquid crystal display device |
KR101697391B1 (en) * | 2013-09-30 | 2017-02-01 | 주식회사 엘지화학 | Copolycarbonate resin and article containing the same |
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Cited By (2)
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EP2243797A1 (en) * | 2008-03-27 | 2010-10-27 | Terumo Kabushiki Kaisha | Bioabsorbable material and device using the same to be placed in the living body |
EP2243797A4 (en) * | 2008-03-27 | 2013-05-01 | Terumo Corp | Bioabsorbable material and device using the same to be placed in the living body |
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FI971834A (en) | 1997-04-30 |
FI971834A0 (en) | 1997-04-29 |
MX9703223A (en) | 1997-07-31 |
EP0789722A1 (en) | 1997-08-20 |
JPH10508064A (en) | 1998-08-04 |
US5614599A (en) | 1997-03-25 |
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