CA2019877A1 - Melt polymerization process for making polyurethanes - Google Patents
Melt polymerization process for making polyurethanesInfo
- Publication number
- CA2019877A1 CA2019877A1 CA002019877A CA2019877A CA2019877A1 CA 2019877 A1 CA2019877 A1 CA 2019877A1 CA 002019877 A CA002019877 A CA 002019877A CA 2019877 A CA2019877 A CA 2019877A CA 2019877 A1 CA2019877 A1 CA 2019877A1
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- Prior art keywords
- process according
- polyol
- zone
- high shear
- molecular weight
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
-
- 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
- C08G18/00—Polymeric products of isocyanates or isothiocyanates
- C08G18/06—Polymeric products of isocyanates or isothiocyanates with compounds having active hydrogen
- C08G18/28—Polymeric products of isocyanates or isothiocyanates with compounds having active hydrogen characterised by the compounds used containing active hydrogen
- C08G18/30—Low-molecular-weight compounds
- C08G18/32—Polyhydroxy compounds; Polyamines; Hydroxyamines
- C08G18/3203—Polyhydroxy compounds
- C08G18/3206—Polyhydroxy compounds aliphatic
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
- B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
- B29C67/00—Shaping techniques not covered by groups B29C39/00 - B29C65/00, B29C70/00 or B29C73/00
- B29C67/24—Shaping techniques not covered by groups B29C39/00 - B29C65/00, B29C70/00 or B29C73/00 characterised by the choice of material
- B29C67/246—Moulding high reactive monomers or prepolymers, e.g. by reaction injection moulding [RIM], liquid injection moulding [LIM]
-
- 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
- C08G18/00—Polymeric products of isocyanates or isothiocyanates
- C08G18/06—Polymeric products of isocyanates or isothiocyanates with compounds having active hydrogen
- C08G18/08—Processes
- C08G18/0895—Manufacture of polymers by continuous processes
-
- 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
- C08G18/00—Polymeric products of isocyanates or isothiocyanates
- C08G18/06—Polymeric products of isocyanates or isothiocyanates with compounds having active hydrogen
- C08G18/28—Polymeric products of isocyanates or isothiocyanates with compounds having active hydrogen characterised by the compounds used containing active hydrogen
- C08G18/30—Low-molecular-weight compounds
- C08G18/32—Polyhydroxy compounds; Polyamines; Hydroxyamines
- C08G18/3203—Polyhydroxy compounds
- C08G18/3212—Polyhydroxy compounds containing cycloaliphatic 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
- C08G18/00—Polymeric products of isocyanates or isothiocyanates
- C08G18/06—Polymeric products of isocyanates or isothiocyanates with compounds having active hydrogen
- C08G18/28—Polymeric products of isocyanates or isothiocyanates with compounds having active hydrogen characterised by the compounds used containing active hydrogen
- C08G18/65—Low-molecular-weight compounds having active hydrogen with high-molecular-weight compounds having active hydrogen
- C08G18/66—Compounds of groups C08G18/42, C08G18/48, or C08G18/52
- C08G18/6666—Compounds of group C08G18/48 or C08G18/52
- C08G18/667—Compounds of group C08G18/48 or C08G18/52 with compounds of group C08G18/32 or polyamines of C08G18/38
- C08G18/6674—Compounds of group C08G18/48 or C08G18/52 with compounds of group C08G18/32 or polyamines of C08G18/38 with compounds of group C08G18/3203
Landscapes
- Chemical & Material Sciences (AREA)
- Health & Medical Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Medicinal Chemistry (AREA)
- Polymers & Plastics (AREA)
- Organic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Polyurethanes Or Polyureas (AREA)
Abstract
ABSTRACT Disclosed is an improved reactive extrusion process for the continuous preparation of a hard polyurethane having Tg values greater than 80°C. The polyisocyanate and polyol ingredients are reacted in a twin-screw extruder which is limited to a single zone of high shear mixing. The present process prevents the formation of small bubbles in the extruded polyurethanes as well as the formation of yellow coloration in what should be an essentially water white polymer, problems which are encountered in the preparation of these hard polyurethanes using the prior art processes wherein the high shear mixing is carried out in multiple zones. 37,052-F
Description
2 ~ 7 ,~
MELT POLYMERIZATION PROCESS FOR MAKING POLYURETHANES
This invention relates to polyurethanes and is more particularly concerned with a process for the preparation of high f]exural modulus polyurethane plastics by reactive extrusion.
U.S. Patents 4,376,834, 4,567,236, and 4,822,827 introduced novel classes of both thermoset and thermoplastic polyurethane polymers to the plastics molding art. These materials are characterized by high impact resistance, stiffness, and other structural strength properties similar to nylon and other engi-neering thermoplastics. Additionally, some members of thi~ group of new materials have exceptionally high Tg values, as high as 165C. The advent of these materials has provided the molding industry with excellent alter-native engineering thermoplastic material choices.
Notably, some of these polyurethanes are thermoplastic and contain little or no soft segment because of either the very minor amount, or, complete absence, of high molecular weight polyol in their formulations. Because of their thermopl~etlc nature and, similarly, to the well known softer thermoplastic polyurethanes, these materials lend themselves to manufacture by the reactive 37,052-F _l_ 2 ~ 7 extrusion process. This method is preferable because of its economic advantages in terms of simply adding the necessa~y ingredients into a sc~ew ~ruder in the absence of solvents and continuously, but rapidly, producing a finished product in the form of desirable profi~e~ or pellets. Such continuous methods are preferably carried out in multi-shaft screw extruders, more preferably twin-screw extruders.
U.S. Patent 3,642,964 and its German counter-part DE 2059570 were the first disclosures to the continuous reactive extrusion of soft thermoplastic polyurethanes in twin-screw extruders. This teaching called for high shear mixing zones in the extruder barrel with each zone having a series of kneading blocks which can have various configurations. More than one such mixing zone or series of blocks is employed on each of the twin-screw shafts. The plurality of mixing zones are either separated by conveying screws or else connected as one long multi-zone depending on the manufacturer's design of the extruder. It will be obvious to one skilled in the art that such extruders must also be equipped with the conventional conveyor screws both in respect of a feed zone and metering zone both before and/or after the mixing zones. Additional types of screws may be employed such as, for example, those which cause backward flow in order to keep mixing zones filled. This process works admirably with soft thermoplastic polyurethanes falling in the hardness range of 60 Shore A to 75 Shore D~
U.S. Patent 3,963,679 dlsc'o3es a proces3 quite similar to the one described above in employing the extrusion apparatus set forth in Figure 1 of its 37,052-F -2-~ ~ ~q ~
disclosure. Primarily, this method differs from that of U.S. Patent ~,642,964 supra in requiring that the poly-urethane forming mixture be subjected to its first hi~h shear mixing during the time it has a viscosity of 10,000 to 100,000 centipoise (lO to lO0 Pa-s). This limitation is paramount to the invention disclosed because when only a single kneading zone is employed after the viscosity has surpassed the upper viscosity limit (Example lb, column 14) the product was inhomogeneous. Similarly, when two zones are employed (Example lc, lines 28 to 38) the product polyurethane is inhomogeneous. Delaying the reaction until the first zone is reached re~ults in the process of the invention as described loccit, lines 40 to 45. This reference inherently calls for more than one zone of high shear mixing with the critical limitation being the placement of the first zone to meet the reaction mixture viscosity range set forth above.
Following the above art, there are a number of disclosures to the reactive extrusion method for pre-paring thermoplastic polyurethanes. U.S. Patent 4,245,081 discloses the continuous preparation using the procedures described in U.S. Patents 3, 642,964 and 3,963,679 discussed supra with the inventive step being the use of a mixture of glycol extenders. U.S. Patents 4,261, 946 and 4,342,847 each disclose essentially the same process differing only in the component 30 proportions. The former is directed to modifying 70 to 98 parts of a thermoplastic polymer with 2 to 30 parts of polyurethane forming components. The procedure is accomplished by adding the thermoplastic polymer, inclusive of preformed polyurethane, and the poly-urethane forming ingredients to the first and second 37 ~ 052-F -3-2 ~ 7 ~
inlets respectively of an extruder. The polyurethane formed insltu in the extruder is inclusive of both those with an~ w out soft segments. The latter has the preformed thermoplastic polymer at 4 to 65 parts with the polyurethane forming components at 35 to 96 parts.
Both patents disclose the use of the same twln-screw technology described in U.S. Patent 3,963,679 supra.
1~ U.S. Patent 4,595,709 discloses a method for converting toluene diisocyanate distillation residues to useful polyurethane polyaddition products containing urethane groups by continuously reacting the residues with low molecular weight compounds containing hydroxyl groups. The reaction is carried out in multiple-screw extruders using the extrusion technology of U.S. Patent 3,963,679 cited supra.
Now the new classes of polyurethanes set forth in the three patents cited supra can be prepared using the twin-screw extruder technology of the prior art discussed aboveO However, there are problem~ encoun-tered which appear to be unique to these new high melt-ing materials. One problem is a tendency for gaseousformation or the appearance of small bubbles in the extruded polymer. Another problem is the formation of yellow coloration in what should be an essentially water white polymer. Part of the problem lies with their high melting characteristics and high melt visco ities. It is a known phenomenon that the polymer chains of thermoplastic polyurethanes can unzip, then ~ip back together dur;ng thermal treatment. Generally speaklng, this is not a problem with the softer polyurethanes made by the prior art processes discussed above. However, in 37,052-F -4-2 ~ r~ 7 the case of these newer materials, the higher temperature required during processing may be the cause of the difficulties. Wh le ~ wishing the present invention to be limited by any theoretical considerations but only by the claims appended herein-b~low, it is believed that during the unzipping and zipping of the polymer chains at the elevated processing temperatures the reformed isocyanate groups can react with each other to form carbodiimide and evolve carbon dioxide thus resulting in bubble formation. The yellow coloration appears to arise from some thermally initiated side-reaction either connected to, or, independent of, the above proposed carbon dioxide formation.
Accordingly, it would be most desirable to have a continuous reactive extrusion process available which could ensure the preparation of these new polyurethane products without the troublesome side ePfects noted above.
The present invention is directed to an improved reactive extrusion process for the continuous preparation of a polyurethane having a Tg greater than 80C from a reaotion mixture comprising a polyisocyanate and at least one polyol component by passing said reac-tion mixture through a twin-screw extruder having besides the feed zone, zones of high shear mixing and a metering zone, wherein the improvement comprises limit-ing the high shear mixing to a single zona.
The polyurethanes ?repared ln accordance with the present invention are substantially free of bubble formation and, surprisingly, are found to be much 37,052-F -5-7 ~
lighter in color than those same chemically constituted polyurethanes but prepared by the prior art method. The difference in color is readily detected by COillpd~ir~g Yellowness Index determinations for the respective samples when measured in accordance with ASTM Test Method D-1925.
Quite unexpectedly, the present reactive extrusion process, if desired, can be carried out at much lower L/D ratios than prior art extrusion methods.
The term L/D ratio refers to the overall length of the twin-screw extruder barrel divided by the barrel diameter, usually measured in millimeters (mm). In running at lower L/D ratios which means shorter barrels, this translates to an additional benefit of lowered energy consumption compared with prior art methods.
Accordingly, the process in accordance with the present invention meets the needs set forth above with the added benefit of lower energy consumption.
The polyurethanes produced in accordance with the present process are made up of either all hard segments or hard segments with only a minor proportion of soft segments arising from the small amount of high molecular weight polyol uqed which is discussed in the art cited supra. They are characterized by the following properties: high impact resistance of at least 1 ft. lb. per inch ~53 J/m), preferably at least 3 ft. lbs. per inch (160 J/m) of notch measured by the notched Izod test in accordance with ASTM D256-56; high heat deflection temperature when subJected to a 251l psl (1.82 MPa) flexural load in accordance with ASTM D648-56 of at least 50C, preferably at least 70C; high flexural 37,052-F -6-2 ~
modulus of at least about 150,000 psi (1034 MPa) as measured by ASTM D790; Tg or secondary transition tempcrat~.e greater than 80C; and hardl~ess values as measured on the Rockwell hardness L ange R (as measured by ASTM D785) of greater than 100~
Additionally, those polyurethanes prepared with non aromatic polyisocyanates are characterized by having essentially optical clarity and light stability.
The products produced in accordance with the present invention find utility, for example, in the molding of under the hood auto and truck parts such as distributor covers, f;lter bowels, air-filter units and covers, containers and covers for electronic circuitry, medical devices requiring transparency and autoclavability, surgical instrument trays and containers for steam sterilization.
Figure l shows in schematic form one typical embodiment of the process of the invention.
The reactive extrusion process in accordance 25 with the present invention is directed primarily to certain specific classeq of hard, high temperature resistant poly~lrethanes defined above. All of the reactants, components, ingredients, and catalysts and proportions therefor have already been set forth in 30 detail in U.S. Patents 4,376,834; 4,567,236; and 4,82Z,827. The compositions include both thermoplastic injection-moldable resins and thermoset resins. The latter are obtained when polyisocyanates, extenders and polyols of functlonalities greater than two are employed as taught in the previously mentioned patents.
37,052-F -7_ ~ g~ h c Q 7 Thermoplastic products are obtained by employing substantially difunctional polyisocyanates and difunctior.al extende.s alld, if used, polyols having functionalities preferably not exceeding about 4. Since the amount by weight of the polyol employed is ~ relatively small9 it is thus possible to employ such components having functionalities greater than two without detracting from the thermoplasticity of the polymer. However, the thermoplastic materials are greatly preferred and in this connection the following sets forth some of the more preferred reactants which can be employed.
Illustrative isocyanates but non-limiting thereof are methylenebis(phenyl isocyanate) including the 4,4'-isomer, the 2,4'-isomer and mixtures thereof, m- and p-phenylene diisocyanates, chloro~henylene diisocyanates, a,~'-xylylene diisocyanate, 2,4- and 2,6--toluene diisocyanate and the mixtures of these latter two isomers which are available commercially, tolidine diisocyanate, hexamethylene diisocyanate, 1,5--naphthalene diisocyanate and isophorone diisocyanate;
cycloaliphatic diisocyanates such as methylenebis(cyclohexyl isocyanate) including the 4,4'--isomer, the 2,4'-isomer and mixtures thereof, and all the geometric isomers thereof including trans/trans, cis/trans, cis/cis and mixtures thereof, cyclohexylene diisocyanate~ (1,2-; 1,3-; or 1,4-), 1-methyl-2,5--cyclohexylene diisocyanate, 1-methyl-2,4-cyclohexylene diisocyanate, 1-methyl-2,6-cyclohexylene diisocyanate, 4,4'-isopropylidenebis(cyclohexyl isocyanate), 4,4'--diisocyanatodicy¢lohexyl, and all geometric isomers and mixtures thereof. Also included are the modified forms of methylenebis(phenyl isocyanate). By the latter are 37,052-F -8-_9_ meant those forms of methylenebis(phenyl isocyanate) which have been treated to render them stable liquids at ambient temperat.lre (clrca 20C). Such piudu~ include those which have been reacted with a minor amount (up to about 0.2 equivalents per equivalent of polyisocyanate) of an aliphat.c glycol or a mixture of aliphatic glycols such as the modified methylenebis(phenyl isocyanates) described in U.S. Patents 3,394,164; 3,644,457;
3,883,571; 4,031,026; 4,115,429; 4,118,411; and 4,299,347. The modified methylenebis(phenyl isocyanates) also include those which have been treated so as to convert a minor proportion of the diisocyanate to the corresponding carbodiimide which then interacts with further diisocyanate to form uretone-imine groups, the resulting product being a stable liquid at ambient temperatures as described, for example, in U.S. Patent 3,384,653. Mixtures of any of the above-named polyiso-cyanates can be employed if desired.
A particularly preferred group of diisocyanates includes aromatic and cycloaliphatic diisocyanates and mixtures thereof as exemplified above. Most preferred species within this group include methylenebis(phenyl isocyanate) including both 4,4'- and 2,4'-isomers and mixtures thereof with 4,4'- preferred, methylenebis-(cyclohexyl isocyanate) including the 4,4'- and 2,4'-isomers and mixtures thereof including all of the geometric isomers thereof with the 4,4'- preferred, and 4,4'-isopropyli~enebis(cyclohexyl isocyanate).
The at least one polyol component called for above in its broadest scope will include the c~ain extender and any polyol if it be employed. In respect of the difunctional extenders, they are not strictly 37,052-F -9-- l o -limited to hydroxyl-containing extenders but can include other active hydrogen materials such as amine groups or ...i:;'u.es of such extender types. r;owever, the preferred extenders compri~e at least one diol having a molecular weight of from 60 to 400. Included in this group are the aliphatic diols having 2 to 1C carbon atoms, inclusive of bis(hydroxyalkyl)cycloalkanes; and the cycloalkane diols described in U.S. Patent 4,822,827 as having 4 to 12 cycloaliphatic carbon atoms.
Illustrative of such diols are ethylene glycol, 1,3--propanediol, 1,4-butanediol. 1,5-pentanediol, 1,6--hexanediol, 1,2-propanediol, 1,3-butanediol, 2,3 -butanediol, 1,3-pentanediol, 1,2-hexanediol, 3--methylpentane-1,5-diol, 1,9-nonanediol, 2-methyloctane--1,8-diol, 1,4-cyclohexanedimethanol, neopentyl glycol, hydroquinone bis(hydroxyethyl)ether, diethylene glycol, dipropylene glycol and tripropylene glycol including mixtures of two or more such diols; 1,2-cyclohexanediol, 1,3-cyclohexanediol, 1,4-cyclohexanediol, 2-cyclohexene--1,4-diol, 2-methyl-1,4-cyclohexanediol, 2-ethyl-1,4--cyclohexanediol, 1,3-cycloheptanediol, 1,4--cycloheptanediol, 2-methyl-1,4-cycloheptanediol and 4-methyl-1, 3-cycloheptanediol; 4,4'--methylenebis(cyclohexanol), 4,4'-methylenebis(2--methyicyclohexanol), 4,4'-methylenebis(3--methylcyclohexanol), 3,3'-methylenebis(cyclohexanol), 4,4'-ethylenebis(cyclohexanol), 4,4'-propylenebis-(cyclohexanol), 4,4'-butylenebis(cyclohexanol), 4,4'--isopropylidenebis(cyclohexanol~, 4,4'-isobutylene-bis(cyclohexanol), 4,4'-dihydroxydicyclohexyl, 4,4'--carbonylbis(cyclohexanol), 3,3'-carbonylbis(cyclo-he~anol); ~'14'-sulfonylbis(cyclohexanol) and 4,4'-oxybis(cyclohexanol); and mixtures of any of the above.
37,052-F -10-2 ~ 7 ~
Preferred for use in the present process are 1,4-butanediol, ',,-;.e~anediol, 1,6-hexanediol, 1,4--cyclohexanedimethanol, the cyclohexanediols including the 1,2-, 1,3-, and 1,4-isomers, and ll,4'-isopropyli-denebis~cyclohexanols), and mixtures c,f the above inaccordance with the teachings of the previously mentione~ patents.
In respect of the polyol component, its use is optional but, even if employed, it will not be present in proportions which would lower the flexural modulus to values below 150,000 psi (1034 MPa) as measured in accordance with ASTM Test Method-D790. Accordingly, the expedient concentration for the polyol falls in the range of from 0 to 25 parts by weight per 100 parts of total urethane reactants ba ed on (i) organic polyisocyanate, (ii) at least one chain extender and said polyol (iii). If it is selected for incorporation for whatever reason, for example, to increase the impact strength, elongation and tensile strength propertie~ of the resulting plastics, then an advantageous range is from 1 to 15 parts per 100 parts of reactants, and preferably from 1 to 5 parts.
Minimum requirements for the polyol component are a molecular weight of at least 500 and functionality of at least 2. Advantageously, the molecular weight falls within a range of from 500 to 12,000 with a functionality of from 2 to not greater than 6;
preferably the molecular weight and functionality are from 500 tc 6,000 and from 2 to 4 respectively; most preferably the functionality is from 2 to 3.
37,052-F -11-2 ~ 7 ~
Exemplary of the classes of polyols which can be optiorally employed are: polyether polyols, poly-ester polyols, hydroxy-terminated p~iy~arbonates~
hydroxy-terminated polybutadienes, hydroxy-terminated polyhutadiene-acrylonitrile copolymers, hydroxy--terminate1 copolymers of dialkyl siloxane and alkylene oxides such as, for example, ethylene oxide and propylene oxide, and mixtures in which any of the above polyols are employed as major component (greater than 50 percent w/w) with amine-terminated polyethers and amino--terminated polybutadiene-acrylonitrile copolymers.
Illustrative of polyether polyols are polyoxy-ethylene glycols, polyoxypropylene glycols which, optionally, have been capped with ethylene oxide resi-dues, random and block copolymers of ethylene oxide and propylene oxide, propoxylated tri- and tetrahydric alcohols such as glycerine, trimethylolpropane and pentaerythritol, which propoxylated compounds have been capped with ethylene oxide, polytetramethylene glycol, random and block copolymers of tetrahydrofuran and ethylene oxide and or propylene oxide, and products derived from any of the above reaction with di- or higher functional carboxylic acids or esters derived from said acids in which latter case ester interchange occurs and the esterifying radicals are replaced by polyether polyol radicals. The preferred polyether polyols are random and block copolymers of ethylene and propylene oxide of functionality fro~ 2 to 4, preferably, 2 to 3 and polytetramethylene glycol polymers of functionality greater than or equal to 2Ø
Generally speaking, the overall proportions of the components (i), (ii), and (iii) are such that the 37,052-F -12-active hydrogen-oontaining components (ii) and (iii) balance the isocyanate component (i) so that stoichio-metric equivalency of the rea~tants is maintained.
However, for various reasons, it is not always possible nor desirable to meet the 1:1 equivalency. Advanta-geously, the proportions are quch that the overall ratioof isocyanate groups to active hydrogen groups is in the range of from 0.90:1 to 1.10:1, preferably, from 0.95:1 to 1.05:1 and, more pre~erably, from 0.98:1 to 1.02:1.
It is frequently desirable, but not essential, to include a catalyst in the process. Any of the cata-lysts conventionally employed in the art to catalyze the reaction of an isocyanate with a reactive hydrogen--containing compound can be employed for this purpose;
see, for example, Saunders et al., Polyurethanes, Chemistry and Technology, Part I, Interscience, New York, 1963, pages 228-232; see also Britain et al., J. Applied Polymer Science, 4, 207-211, 1960. Such catalysts include organic and inorganic acid salts of, and organometallic derivatives of, bismuth, lead, tin, iron, antimony, uranium, cadmium, cobalt, thorium, aluminum, mercury, zinc, nickel cerium, molybdenum, vanadium, copper, manganese and zirconium, as well as phosphines and tertiary organic amines. Representative organotin catalysts are stannous octoate 7 stannous oleate, dibutyltin dioctoate and dibutyltin dilaurate.
Representative tertiary organic amine catalysts are triethylamine, triethylenediamine, N,N,N',N'--tetramethylethylenediamine, N,N,N',N'-tetraethyl-ethylenediamine, N-methylmorpholine, N-ethylmorpholine, N,N,N',N'-tetramethylguanidine, N,N,N',N'-tetramethyl--1,3-butanediamine, N,N-dimethylethanolamine and N~N--diethylethanolamine. The amount of catalyst employed 37,352-F -13-éj 7 is generally within the range of from 0.02 to 2.0 percent by weight based on the total weight of the reactants.
Included in the process is the one-shot procedure, wherein all the reactants are brou@h~L
together all at once in the extrusion apparatus, and the prepolymer or quasi-prepolymer techniques. The use of a prepolymer technique would, of course, be limited primarily to those formulations employing the polyol component (iii) wherein part or all of the polyol is first reacted with isocyanate and the isocyanate prepolymer, then fed to the extrusion apparatus along with the extender. However, the preferred method is the one-shot reaction.
Additionally, the process can also include various additives such as impact modifiers, fillers and fiber glass; antioxidants, pigments, fire retardants, plasticizers, reinforcing agents and W2X lubricants commonly employed in the art in such compositions.
These may be added along with the reactants or at a later stage through a downstream feed port, or at a post reactor compounding step.
The process in accordance with the present invention is carried out by feeding the above ingre-dients into a commercial multi-screw extruder which is, generally speaking, a twin-screw extruder. The screws can be co- or counter-rotating. Preferably, a co--rotating and self-cleaning twin-screw extruder is employed. The general procedures and extrusion equipmer.t described in U.SO Patents 3,642,964 and 3,963,67g can be employed herein except for the novel 37,052-F -14-¢; ~ ~
exceptions discussed hereinbelow. Generally speaking, the reactive extrusion process is carried out within an overall temperature ran~e of f~ " , 5aoc tG 280C. That is to say, individual zones may not all be at the same temperatures but their individual values will fall with n this range.
The reactants can be measured out using known means such as, for example, gear pumps, membrane or piston pumps for delivery to the extruder feed zone.
Figure 1 shows one schematic embodiment of the process wherein (A), (B), and (C) represent three separate reactant feed lines for the isocyanate component, polyol component~ and catalyst component respectively. It is not essential that all three lines be utilized. For example, catalyst may be included in the (B) feed line;
alternatively, and, if desired, the reactants may be mixed in a suitable mixing head before they are introduced into the extruder. In that case, (A) represents a mixing head which includes all the reactants with catalyst or else the catalyst may be added separately as (B). One of the advantages of the present process i5 that viscosity build-up of the reaction mixture in the FEED ZONE is not in any way a particular problem. In fact, one of the key features of the present process i3 that the reaction mixture viscosity should exceed 100,000 cps (~00 Pas) before reaching the critical SINGLE HIGH SHEAR MIXING ZONE
(hereinafter MIXING ZONE). In this regard, the gel time for the reactant systems should be less than about 10 seconds, preferably less than about 6 seconds and FEED
ZONE temperatures can fall wlthi~. a range of from 150C
to 250C. he FEED ZONE length and conveying screws are in no way critical to the present process and can be 37,052-F -15-2 ~
configured as in the previously mentioned U.S. patents.
Actual barrel lengths for the FEED ZONE will be defined by ~he overall L/D (lengt;l/diameter) of the ext~uder which will be discussed in detail below.
Besides the diff~rences in the reaction mix viscosities in the FEED ZONES between the present process and the prior art cited supra particularly U.S.
Patent 3,~63,679, the limitation o~ the present MIXING
ZONE to one single zone o~ high shear mixing is a very critical and novel ~eature which results in polymer improvements that otherwise cannot be obtained with the hard polyurethanes. Such multiple zones of high shear mixing are described in detail in the previously mentioned patents, particularly the '679 reference.
Generally speaking, such high shear mixing zones employ two series of broad edged multiple kneading elements or blocks mounted in intermeshing relationship on the pair of parallel mounted screws in the twin-screw extruder in each zone. The individual kneading elements or blocks can be triangular, circular or elliptical as typically disclosed in the figures 2 through 7 of the '679 patent.
The dimensions are such that there is minimal radial clearance between the inner surface of the barrel and the perimeter edges of the blocks. Hence, rotation of the screws subjects the reaction mixture to high shear force~. Additional mixing and application of high shear forces can be imparted, if desired, by mounting appropriate baffles but more usually reverse pitch kneading blocks. Generally speaking, conveying screws are present in the same extruder barrel sections which contain the zone of kneading blocks.
37,052-F -16-What distinguishes the present process is the fact that the high shear mixing is carried out in just a single ~ uf these multiple kneading elements and not a series of repetitive zones. Advantageously, the actual length of the kneading elements within the single zone will fall within a range of from 60 ~n. to 240 mm, preferably from 80 to 180, and more preferably from 120 to 180 mm.
In order to provide sufficient shearing forces in the polymer forming mixture, a sufficiently high shear rate or velocity gradient must be achieved.
Generally speaking, this is related to the combination of the minimal radial clearances between the barrel (extruder wall) and shearing edges of the blocks referred to above and the speed of screw rotation.
Advantageously, this clearance will fall within a range of from 0.05 nm to 0.6 mm, preferably from 0.1 to 0.4 mm. Screw rotation expressed in rotations per minute (r.p.m.) will fall within a range of from 140 to 500 r.p.m., preferably 150 to 300 r.p.m.
Temperatures in the MIXING ZONE will be controlled within a range similar to the FEED ZONE with optionally a slightly higher range, that is to say, from 150C to 280C. Capability of cooling this zone should be provided in the event that exotherm could exceed the upper limit of 280C.
The EXTRUSION ZONE, sometimes called the METERING ZONE, can be configured similarly to the prior art w th onl~ conveying screws. Temperatures are advantageously controlled to a range of from 180C to 280C. The reacted melt product is simply extruded at 37,052-F -17-the end through any desired molding tool or die known to the art such as, for example, slot dies, profile-forming ules and rods.
There is no particular limit on overall barrel ength other than what is dictated by practical con-siderations. However, a particularly attractive feature of the present process are the short barrel lengths which are possible. Advantageously, the L/D ratio can fall within a range of from 10/1 to 44/l, preferably from 15/1 to 25/1, most preferably from 15/l to 20/l.
Overall temperature control throughout the above L/D
ranges, whether it be through heating and/or cooling in particular zones, will fall within the previously stated range of from 150C to 280C. Overall residence times in the extruder when operating under these L/D, temperature, and r.p.m. conditions set forth above will fall within a range of from 5 to 45 seconds, preferably from 6 to 30 seconds, more preferably from 6 to 25 seconds.
The extruded polyurethanes can be in finally desired shape or else comminuted or pelletized for further molding or injection molding into desired article~. The polymers a3 obtained need no further treatment, havin~ attained their superior physical and mechanical properties as set forth in the three patents cited supra and already incorporated herein.
The following examples describe the manner and process of making and using the invention and set forth the best mode cor.templated by the inventors of carrying 37,052-F -18-_19_ out the invention but are not to be construed as limit-ing.
Exam~le 1 The following experiment sets forth a com-parison of two redc~ive extrusion methods, one in accordance with the invention (run 1) and the other (comparison 1? in accordance with the prior art.
A Werner and Pfleiderer ZSK-53 self-cleaning, co-rotating twin-screw extruder was fitted with five barrels of which four had high shear mixing zones. Each of the latter zones were 240 mm in length but only 120 mm of this length was formed of the actual high shear kneading blocks themselves with the remainder given over to conveying screws. Radial clearance between extruder wall and outer diameter of the shearing edges of each kneading block was about 0.2 mm. Screw speed was con-trolled to 460 r.p.m. Extruder temperatures were con-trolled by five independent barrel heating or cooling zones. Feed zone temperature was 225 + 5C, with extrusion zone being 215 ~ 5C and the intermediate zones including the four high shear mixing zones being 190 to 210C. ~ sheeting die, 200 mm width and 3 mm gap was flanged to the end of the extrusion zone.
For comparison 1, a mixture in the proportional pa~ts by weight of 100 part~ of 1,4-cyclohexanedi-3 methanol, 0.82 parts of trisnonylphenyl phosphite and0.69 parts of Irganox 1010 (antioxidant supplied by Ciba Geigy Corp.) was degassed and dehydrated under vacuum at 99C for 2 hours. Using a gear pump, this mixture was delivered to the front feed port of the extruder. This means that the length/diameter ~L/D) ratio for this feed 37,052-F -19_ passing through the 2344 mm of length for the five zones of the barrel was 44/1. A second gear pump delivered to ''-.e s~ e ront feed port 175.2 parts of~ melted 4,4'--methylenebis(phenyl isocyanate) per 100 parts of the above diol,-while a third pump delivered at the same proportional rate 0.33 part of a polyurethane catalyst Fomrez UL-22 which is dimethyltindidodecyl mercaptide supplied by Witco Corporation. Gel time of this reacting mixture determined by hand mixing the components rapidly in a beaker was less than 10 seconds.
The polymer was extruded onto a retal conveyor belt at 26C, cooled and diced. At this point the solidified polymer was observed for the formation of bubbles.
After drying at 115C in a dehumidifying hopper dryer with a dew point below -28C, the pellets were injection molded into test specimens. Their physical properties were determined according to ASTM test procedures with the results set forth in Table I.
Run 1 in accordance with the invention was carried out identically to the above comparison run in every respect except the reactant~ were fed into a downstream feed port. The second feed port was located in the extruder barrel which was just prior to the la~t (i.e. fourth) high shear mixing zone. Feeding the reactants at this point shortened the barrel to 919 mm and reduced the L/D to 17.3/1. More importantly, the reaction mixture passed through a single zone of high shear mixing wherein the actual length of kneading blocks was 120 mm.
Comp2riscn of the two extrudates showed run 1 to be essentially clear with the presence of very few minute bubbles, essentially no more than what are to be 37,052-F -20-2 ~
expected in the extrusion of transparent type thermo-plastics. Contrastingly~ Comparison 1 showed copious bubbles in the sol~dLl . Gd eAtrudate. In respect of color formation as measured by Yellowness Index, run 1 was much lower in color compared with comparison 1. As for molecular weights and other physical properties, ru~
1 appeared to be superior in most respects.
37,052-F -21-~ :?~
Run Comp. 1 Polymer M.W.l 232,432 286,654 5 Flex Modulus, psi ~- 103 (GPa) 311.3 (2.15) 305.0 (2.1) Flex strength, psi (MPa) 14,714 (101.4) 14,898 (102.7) Tensile strength, psi (MPa) Yield 11,624 (80.1) 11,634 (80.2) 10 8reak 8,634 (59.5) 9,086 (62.6) Tensile moduius, psi x 103 (GPa) 293.4 (2.02) 289.2 (1.99) Elongation (~) Yield 8.2 8.3 8reak 34.6 31.0 HDT2 ( C ) 66 psi (455 kPa) 133 135 264 psi (1820 kPa) 123 123 Notched Izod3 ft-lbs/in (J~m) notch 1/8" (3.175 mm) thick sample 1.10 (58.7) 1.24 (66.2) 1/4" (6.35 mm)thick sample 0.74 (39.5~ 1.40 (74.7) Yellowness IndeY4 3.05 5.75 ~ubble Formation5 copious very few bubbles bubbles Footnotes to TALLL I
-1 Polymer weight average molecular weight determined by gel permeation chromatography using a polystyrene reference as standard.
30 2 ~DT: Heat deflectiun temperature measured at the specified pressures in accordan~e with AST~ Test Method D-648.
3 Notched Izod: Izod impact strength measured on 1/8" and 1~4"
(3.175 mm and 6.35 mm) thick samples in accordance with ASTM
D256-56.
37, 052-F -22-r~
4 Yellowness Index: determined usinq ASTM D-1925 standard at a two degree observer angle using a Pacific Scientific Spectrogard Color Syste~, Silve~ Spring, Marylan~ 20910 with the illuminant being simul~ted average daylight.
5 Bubble Formation: refers to the qualitative visual observation of the extruded polymer for th~ formation o^ bubbles; presence of a very few minute b~bbles can be tole~ated ~Ind the polymers classified as essentially a ~lear plastic, ~hereas the formation of a copio~s number of bubbles is not accep`:able.
Example 2 Similarly to Example 1~ this experiment describes comparison 2 and run 2 reactive extrusions wherein the same apparatus and conditions were employed herein with the exception of different reactant com-ponents.
The mixture pumped to the first feed port for comparison 2 which ran through the four mixing zones was as follows: a degassed and dehydrated mixture of 100 parts of an 85/15 mole ratio of 1,4-cyclohexane-dimethanol and hydrogenated bisphenol-A, 0.77 parts trisnonylphenyl phosphite, and 0.64 parts of Irganox 1010; 158.35 parts of melted 4,4'-methylenebis(phenyl isocyanate); and 0.31 part of Fomrez UL-22. For run 2 which ran through only the ~ingle zone of high shear mixing, the same three part ingredient mixture was fed into the downstream feed port for the L/D ratio of 17.3i1.
The properties of the injection molded samples from the two runs are set forth in Table II. Signifi-c~rtly less gassing in the initial extrudate and lower color for molded run 2 specimens compared to comparison 37,052-F -23-2 0 ~ 7 ~
2 was observed. Their physical properties were essentially comparable.
Run Comp. 2 2 Polymer M.W. 203,761 212,193 Fles Modulus, psi x 103 (GPa) 320.6 (2.Zl) 311.6 (2.14) Flex strength, psi (MPa) 12,918 (89~ 12,812 (88) 10 Tensile strength, psi (MPa) Yield 11,887 (82) 11,825 (81.5) Break 8,729 (60.2) 8,664 (59.7) Tensile modulus, (psi x 103) 295.8 (2.04) 291.4 (2.01) Elongation (~) Yield 8.3 8.2 Break 22.1 24.9 ~DT (~C) 66 psi (455 kPa) 145 145 264 psi (1820 kPa) 135 139 Notched Izod ft-lbs/in (J/m) notch 1/8" (3.175 mm) thick sample 1.15 ~61.4) 1.02 (54.4) 1/4" (6.35 mm) thick sample 0.82 (43.8) 0.93 (49.6) 25 Yellowness Index 8.13 5.64 Subble Formation copious very few bubbles bubbles 3 Example 3 This experiment similar to those above compared the properties of the extrudates and the injection molded samples ~rom comparison 3 and run 3. Using the same extruder configurations and conditions set forth in 37,052-F -24-2 ~
Example 1, the comparison 3 ingredients were fed into the front feed port of the extruder barrel while the same ingredients were fed into tile uownsiream feed port for run 3 with the latter having only the single zone of high shear mixing. The ingredients were as follows:
degassed and dehydrated mixture of 100 parts of 1,6--hexanediol, 0.94 part trisnonylphenyl phosphite, and 0.78 part of Irganox 1010; 213.8 part of melted 4,4'--methylenebis(phenyl isocyanate); and 0.19 part of Fomrez UL-22.
The properties of the two product runs are set forth in Table III. The data show significantly less gassing and lower color for run 3 compared with its comparison sample.
3o 37,052-F -25-`2~
TABLE III
Run Comp. 3 3 -- , , .
PolymPr K.W. 583,000 642,500 5 Tensile strength, psi (MPa) Yield 8960 (61.8) 7650 (52.7) Break 6600 (45.5) 9865 (68) Tensile modulus, psi x 103 (GPa) 256 (1.77) 273 (1.88) Elongation (~) Yield 7 Break 27 166 HDT (C) 66 psi (455 kPa) 88 86 264 psi (1820 kPa) 75 76 Notched Izod ft-lbs~in (J/m) notch 1/8" (3.175 mm) thick sample 1.747 (93.3) 2.399 (128) 1/4" (6.35 mm) thi~k sample 1.294 (69.1) 1.782 (95.1) Bubble Formation COPIOUS VERY FEW
- BU~BLES ~UB8LES
EXample 4 This example describes the preparation of a hard thermoplastic polyurethane polymer in accordance with the present invention ~run 4) and comparison 4.
In run 4, a self-cleaning twin-screw Werner and Pfleiderer ZSK-120V was employed with a single zone of high shear mixing at an L/D ratio of 9.5/1 from the feed port and with an overall extruder L/D of 18.8/1. The actual length of kneading blocks in the high shear 37,052-F -26-mixing zone was 180 mm. Screw speed was 250 r.p.m. and with about 0.2 mm radial clearance between extruder wall and outei~ dia,l-eLe} of the shearing edges of each kneading block. Zone temperatures were feed, 188C;
mixing, 177 to 199C; and extrusion, 2300.
The reaction mixture ~hich was metered into the feed port in three streams in the following proportions in parts by weight was as follows: degassed and dehydrated mixture of 43.2 parts of 1,4-cyclohexane-dimethanol, 23.6 parts of 1,6-hexanediol 10.4 parts of a 650 molecular weight polytetramethylene glycol, 0.52 part of Irganox 1010, and 0.31 part of triphenyl phosphite; 130.79 parts of 4,4-methylenebis(phenyl isocyanate); and 0.10 part of a 50/50 weight mixture of stannous octoate and dioctyl phthalate. The extruded product was fed onto a cool conveyor as described in the previous examples and dicedO The extruded material was clear transparent with only a few minute bubbles being detectable. The injection molded product had the following properties set forth in Table IV.
Comparison 4 was carried out under essentially the same temperature conditions with identical ingredients to run 4 but using a twin-screw Werner and Pfleiderer extruder having an 83 mm diameter, equipped with three zones of high shear mixing and an L/D of 30~7/1.
3o A comparison of the two runs shows that run 4 provided a product with much superior molecular weight to the compar-son run ~ znd a measurably better yellow index and transmission. Notably, this was accomplished 37,052-F -27-20~ 9~rlJ7 with much less power consumption as compared with co~parison 4.
TABLE IV
Run Comp. 4 4 .
Polymer M.W. 266,302 359,352 Tensile Strength, psi (MPa) Yield 10,305 9,896 Break 7,867 7,703 Tensile Modulus, psi x 103 (GPa) 274 (1.89) 274.8 (1.9) Elongation (~) Yield 6.4 5.7 Break 42 45 Yellowness Index 5.52 4.74 Transmission at 380 NMl 58.05~ 61.97 Footnote to Table IV
1 Light transmittance in percent measured on injection molded disk measuring 2 inches (51 mm) diameter x 1/8" (3.2 mm) thick at 380 nanometers using Pacific Scientific Spectrogard Color Systems, Silver Spring, Maryland, 20910.
37, 052-F -28-
MELT POLYMERIZATION PROCESS FOR MAKING POLYURETHANES
This invention relates to polyurethanes and is more particularly concerned with a process for the preparation of high f]exural modulus polyurethane plastics by reactive extrusion.
U.S. Patents 4,376,834, 4,567,236, and 4,822,827 introduced novel classes of both thermoset and thermoplastic polyurethane polymers to the plastics molding art. These materials are characterized by high impact resistance, stiffness, and other structural strength properties similar to nylon and other engi-neering thermoplastics. Additionally, some members of thi~ group of new materials have exceptionally high Tg values, as high as 165C. The advent of these materials has provided the molding industry with excellent alter-native engineering thermoplastic material choices.
Notably, some of these polyurethanes are thermoplastic and contain little or no soft segment because of either the very minor amount, or, complete absence, of high molecular weight polyol in their formulations. Because of their thermopl~etlc nature and, similarly, to the well known softer thermoplastic polyurethanes, these materials lend themselves to manufacture by the reactive 37,052-F _l_ 2 ~ 7 extrusion process. This method is preferable because of its economic advantages in terms of simply adding the necessa~y ingredients into a sc~ew ~ruder in the absence of solvents and continuously, but rapidly, producing a finished product in the form of desirable profi~e~ or pellets. Such continuous methods are preferably carried out in multi-shaft screw extruders, more preferably twin-screw extruders.
U.S. Patent 3,642,964 and its German counter-part DE 2059570 were the first disclosures to the continuous reactive extrusion of soft thermoplastic polyurethanes in twin-screw extruders. This teaching called for high shear mixing zones in the extruder barrel with each zone having a series of kneading blocks which can have various configurations. More than one such mixing zone or series of blocks is employed on each of the twin-screw shafts. The plurality of mixing zones are either separated by conveying screws or else connected as one long multi-zone depending on the manufacturer's design of the extruder. It will be obvious to one skilled in the art that such extruders must also be equipped with the conventional conveyor screws both in respect of a feed zone and metering zone both before and/or after the mixing zones. Additional types of screws may be employed such as, for example, those which cause backward flow in order to keep mixing zones filled. This process works admirably with soft thermoplastic polyurethanes falling in the hardness range of 60 Shore A to 75 Shore D~
U.S. Patent 3,963,679 dlsc'o3es a proces3 quite similar to the one described above in employing the extrusion apparatus set forth in Figure 1 of its 37,052-F -2-~ ~ ~q ~
disclosure. Primarily, this method differs from that of U.S. Patent ~,642,964 supra in requiring that the poly-urethane forming mixture be subjected to its first hi~h shear mixing during the time it has a viscosity of 10,000 to 100,000 centipoise (lO to lO0 Pa-s). This limitation is paramount to the invention disclosed because when only a single kneading zone is employed after the viscosity has surpassed the upper viscosity limit (Example lb, column 14) the product was inhomogeneous. Similarly, when two zones are employed (Example lc, lines 28 to 38) the product polyurethane is inhomogeneous. Delaying the reaction until the first zone is reached re~ults in the process of the invention as described loccit, lines 40 to 45. This reference inherently calls for more than one zone of high shear mixing with the critical limitation being the placement of the first zone to meet the reaction mixture viscosity range set forth above.
Following the above art, there are a number of disclosures to the reactive extrusion method for pre-paring thermoplastic polyurethanes. U.S. Patent 4,245,081 discloses the continuous preparation using the procedures described in U.S. Patents 3, 642,964 and 3,963,679 discussed supra with the inventive step being the use of a mixture of glycol extenders. U.S. Patents 4,261, 946 and 4,342,847 each disclose essentially the same process differing only in the component 30 proportions. The former is directed to modifying 70 to 98 parts of a thermoplastic polymer with 2 to 30 parts of polyurethane forming components. The procedure is accomplished by adding the thermoplastic polymer, inclusive of preformed polyurethane, and the poly-urethane forming ingredients to the first and second 37 ~ 052-F -3-2 ~ 7 ~
inlets respectively of an extruder. The polyurethane formed insltu in the extruder is inclusive of both those with an~ w out soft segments. The latter has the preformed thermoplastic polymer at 4 to 65 parts with the polyurethane forming components at 35 to 96 parts.
Both patents disclose the use of the same twln-screw technology described in U.S. Patent 3,963,679 supra.
1~ U.S. Patent 4,595,709 discloses a method for converting toluene diisocyanate distillation residues to useful polyurethane polyaddition products containing urethane groups by continuously reacting the residues with low molecular weight compounds containing hydroxyl groups. The reaction is carried out in multiple-screw extruders using the extrusion technology of U.S. Patent 3,963,679 cited supra.
Now the new classes of polyurethanes set forth in the three patents cited supra can be prepared using the twin-screw extruder technology of the prior art discussed aboveO However, there are problem~ encoun-tered which appear to be unique to these new high melt-ing materials. One problem is a tendency for gaseousformation or the appearance of small bubbles in the extruded polymer. Another problem is the formation of yellow coloration in what should be an essentially water white polymer. Part of the problem lies with their high melting characteristics and high melt visco ities. It is a known phenomenon that the polymer chains of thermoplastic polyurethanes can unzip, then ~ip back together dur;ng thermal treatment. Generally speaklng, this is not a problem with the softer polyurethanes made by the prior art processes discussed above. However, in 37,052-F -4-2 ~ r~ 7 the case of these newer materials, the higher temperature required during processing may be the cause of the difficulties. Wh le ~ wishing the present invention to be limited by any theoretical considerations but only by the claims appended herein-b~low, it is believed that during the unzipping and zipping of the polymer chains at the elevated processing temperatures the reformed isocyanate groups can react with each other to form carbodiimide and evolve carbon dioxide thus resulting in bubble formation. The yellow coloration appears to arise from some thermally initiated side-reaction either connected to, or, independent of, the above proposed carbon dioxide formation.
Accordingly, it would be most desirable to have a continuous reactive extrusion process available which could ensure the preparation of these new polyurethane products without the troublesome side ePfects noted above.
The present invention is directed to an improved reactive extrusion process for the continuous preparation of a polyurethane having a Tg greater than 80C from a reaotion mixture comprising a polyisocyanate and at least one polyol component by passing said reac-tion mixture through a twin-screw extruder having besides the feed zone, zones of high shear mixing and a metering zone, wherein the improvement comprises limit-ing the high shear mixing to a single zona.
The polyurethanes ?repared ln accordance with the present invention are substantially free of bubble formation and, surprisingly, are found to be much 37,052-F -5-7 ~
lighter in color than those same chemically constituted polyurethanes but prepared by the prior art method. The difference in color is readily detected by COillpd~ir~g Yellowness Index determinations for the respective samples when measured in accordance with ASTM Test Method D-1925.
Quite unexpectedly, the present reactive extrusion process, if desired, can be carried out at much lower L/D ratios than prior art extrusion methods.
The term L/D ratio refers to the overall length of the twin-screw extruder barrel divided by the barrel diameter, usually measured in millimeters (mm). In running at lower L/D ratios which means shorter barrels, this translates to an additional benefit of lowered energy consumption compared with prior art methods.
Accordingly, the process in accordance with the present invention meets the needs set forth above with the added benefit of lower energy consumption.
The polyurethanes produced in accordance with the present process are made up of either all hard segments or hard segments with only a minor proportion of soft segments arising from the small amount of high molecular weight polyol uqed which is discussed in the art cited supra. They are characterized by the following properties: high impact resistance of at least 1 ft. lb. per inch ~53 J/m), preferably at least 3 ft. lbs. per inch (160 J/m) of notch measured by the notched Izod test in accordance with ASTM D256-56; high heat deflection temperature when subJected to a 251l psl (1.82 MPa) flexural load in accordance with ASTM D648-56 of at least 50C, preferably at least 70C; high flexural 37,052-F -6-2 ~
modulus of at least about 150,000 psi (1034 MPa) as measured by ASTM D790; Tg or secondary transition tempcrat~.e greater than 80C; and hardl~ess values as measured on the Rockwell hardness L ange R (as measured by ASTM D785) of greater than 100~
Additionally, those polyurethanes prepared with non aromatic polyisocyanates are characterized by having essentially optical clarity and light stability.
The products produced in accordance with the present invention find utility, for example, in the molding of under the hood auto and truck parts such as distributor covers, f;lter bowels, air-filter units and covers, containers and covers for electronic circuitry, medical devices requiring transparency and autoclavability, surgical instrument trays and containers for steam sterilization.
Figure l shows in schematic form one typical embodiment of the process of the invention.
The reactive extrusion process in accordance 25 with the present invention is directed primarily to certain specific classeq of hard, high temperature resistant poly~lrethanes defined above. All of the reactants, components, ingredients, and catalysts and proportions therefor have already been set forth in 30 detail in U.S. Patents 4,376,834; 4,567,236; and 4,82Z,827. The compositions include both thermoplastic injection-moldable resins and thermoset resins. The latter are obtained when polyisocyanates, extenders and polyols of functlonalities greater than two are employed as taught in the previously mentioned patents.
37,052-F -7_ ~ g~ h c Q 7 Thermoplastic products are obtained by employing substantially difunctional polyisocyanates and difunctior.al extende.s alld, if used, polyols having functionalities preferably not exceeding about 4. Since the amount by weight of the polyol employed is ~ relatively small9 it is thus possible to employ such components having functionalities greater than two without detracting from the thermoplasticity of the polymer. However, the thermoplastic materials are greatly preferred and in this connection the following sets forth some of the more preferred reactants which can be employed.
Illustrative isocyanates but non-limiting thereof are methylenebis(phenyl isocyanate) including the 4,4'-isomer, the 2,4'-isomer and mixtures thereof, m- and p-phenylene diisocyanates, chloro~henylene diisocyanates, a,~'-xylylene diisocyanate, 2,4- and 2,6--toluene diisocyanate and the mixtures of these latter two isomers which are available commercially, tolidine diisocyanate, hexamethylene diisocyanate, 1,5--naphthalene diisocyanate and isophorone diisocyanate;
cycloaliphatic diisocyanates such as methylenebis(cyclohexyl isocyanate) including the 4,4'--isomer, the 2,4'-isomer and mixtures thereof, and all the geometric isomers thereof including trans/trans, cis/trans, cis/cis and mixtures thereof, cyclohexylene diisocyanate~ (1,2-; 1,3-; or 1,4-), 1-methyl-2,5--cyclohexylene diisocyanate, 1-methyl-2,4-cyclohexylene diisocyanate, 1-methyl-2,6-cyclohexylene diisocyanate, 4,4'-isopropylidenebis(cyclohexyl isocyanate), 4,4'--diisocyanatodicy¢lohexyl, and all geometric isomers and mixtures thereof. Also included are the modified forms of methylenebis(phenyl isocyanate). By the latter are 37,052-F -8-_9_ meant those forms of methylenebis(phenyl isocyanate) which have been treated to render them stable liquids at ambient temperat.lre (clrca 20C). Such piudu~ include those which have been reacted with a minor amount (up to about 0.2 equivalents per equivalent of polyisocyanate) of an aliphat.c glycol or a mixture of aliphatic glycols such as the modified methylenebis(phenyl isocyanates) described in U.S. Patents 3,394,164; 3,644,457;
3,883,571; 4,031,026; 4,115,429; 4,118,411; and 4,299,347. The modified methylenebis(phenyl isocyanates) also include those which have been treated so as to convert a minor proportion of the diisocyanate to the corresponding carbodiimide which then interacts with further diisocyanate to form uretone-imine groups, the resulting product being a stable liquid at ambient temperatures as described, for example, in U.S. Patent 3,384,653. Mixtures of any of the above-named polyiso-cyanates can be employed if desired.
A particularly preferred group of diisocyanates includes aromatic and cycloaliphatic diisocyanates and mixtures thereof as exemplified above. Most preferred species within this group include methylenebis(phenyl isocyanate) including both 4,4'- and 2,4'-isomers and mixtures thereof with 4,4'- preferred, methylenebis-(cyclohexyl isocyanate) including the 4,4'- and 2,4'-isomers and mixtures thereof including all of the geometric isomers thereof with the 4,4'- preferred, and 4,4'-isopropyli~enebis(cyclohexyl isocyanate).
The at least one polyol component called for above in its broadest scope will include the c~ain extender and any polyol if it be employed. In respect of the difunctional extenders, they are not strictly 37,052-F -9-- l o -limited to hydroxyl-containing extenders but can include other active hydrogen materials such as amine groups or ...i:;'u.es of such extender types. r;owever, the preferred extenders compri~e at least one diol having a molecular weight of from 60 to 400. Included in this group are the aliphatic diols having 2 to 1C carbon atoms, inclusive of bis(hydroxyalkyl)cycloalkanes; and the cycloalkane diols described in U.S. Patent 4,822,827 as having 4 to 12 cycloaliphatic carbon atoms.
Illustrative of such diols are ethylene glycol, 1,3--propanediol, 1,4-butanediol. 1,5-pentanediol, 1,6--hexanediol, 1,2-propanediol, 1,3-butanediol, 2,3 -butanediol, 1,3-pentanediol, 1,2-hexanediol, 3--methylpentane-1,5-diol, 1,9-nonanediol, 2-methyloctane--1,8-diol, 1,4-cyclohexanedimethanol, neopentyl glycol, hydroquinone bis(hydroxyethyl)ether, diethylene glycol, dipropylene glycol and tripropylene glycol including mixtures of two or more such diols; 1,2-cyclohexanediol, 1,3-cyclohexanediol, 1,4-cyclohexanediol, 2-cyclohexene--1,4-diol, 2-methyl-1,4-cyclohexanediol, 2-ethyl-1,4--cyclohexanediol, 1,3-cycloheptanediol, 1,4--cycloheptanediol, 2-methyl-1,4-cycloheptanediol and 4-methyl-1, 3-cycloheptanediol; 4,4'--methylenebis(cyclohexanol), 4,4'-methylenebis(2--methyicyclohexanol), 4,4'-methylenebis(3--methylcyclohexanol), 3,3'-methylenebis(cyclohexanol), 4,4'-ethylenebis(cyclohexanol), 4,4'-propylenebis-(cyclohexanol), 4,4'-butylenebis(cyclohexanol), 4,4'--isopropylidenebis(cyclohexanol~, 4,4'-isobutylene-bis(cyclohexanol), 4,4'-dihydroxydicyclohexyl, 4,4'--carbonylbis(cyclohexanol), 3,3'-carbonylbis(cyclo-he~anol); ~'14'-sulfonylbis(cyclohexanol) and 4,4'-oxybis(cyclohexanol); and mixtures of any of the above.
37,052-F -10-2 ~ 7 ~
Preferred for use in the present process are 1,4-butanediol, ',,-;.e~anediol, 1,6-hexanediol, 1,4--cyclohexanedimethanol, the cyclohexanediols including the 1,2-, 1,3-, and 1,4-isomers, and ll,4'-isopropyli-denebis~cyclohexanols), and mixtures c,f the above inaccordance with the teachings of the previously mentione~ patents.
In respect of the polyol component, its use is optional but, even if employed, it will not be present in proportions which would lower the flexural modulus to values below 150,000 psi (1034 MPa) as measured in accordance with ASTM Test Method-D790. Accordingly, the expedient concentration for the polyol falls in the range of from 0 to 25 parts by weight per 100 parts of total urethane reactants ba ed on (i) organic polyisocyanate, (ii) at least one chain extender and said polyol (iii). If it is selected for incorporation for whatever reason, for example, to increase the impact strength, elongation and tensile strength propertie~ of the resulting plastics, then an advantageous range is from 1 to 15 parts per 100 parts of reactants, and preferably from 1 to 5 parts.
Minimum requirements for the polyol component are a molecular weight of at least 500 and functionality of at least 2. Advantageously, the molecular weight falls within a range of from 500 to 12,000 with a functionality of from 2 to not greater than 6;
preferably the molecular weight and functionality are from 500 tc 6,000 and from 2 to 4 respectively; most preferably the functionality is from 2 to 3.
37,052-F -11-2 ~ 7 ~
Exemplary of the classes of polyols which can be optiorally employed are: polyether polyols, poly-ester polyols, hydroxy-terminated p~iy~arbonates~
hydroxy-terminated polybutadienes, hydroxy-terminated polyhutadiene-acrylonitrile copolymers, hydroxy--terminate1 copolymers of dialkyl siloxane and alkylene oxides such as, for example, ethylene oxide and propylene oxide, and mixtures in which any of the above polyols are employed as major component (greater than 50 percent w/w) with amine-terminated polyethers and amino--terminated polybutadiene-acrylonitrile copolymers.
Illustrative of polyether polyols are polyoxy-ethylene glycols, polyoxypropylene glycols which, optionally, have been capped with ethylene oxide resi-dues, random and block copolymers of ethylene oxide and propylene oxide, propoxylated tri- and tetrahydric alcohols such as glycerine, trimethylolpropane and pentaerythritol, which propoxylated compounds have been capped with ethylene oxide, polytetramethylene glycol, random and block copolymers of tetrahydrofuran and ethylene oxide and or propylene oxide, and products derived from any of the above reaction with di- or higher functional carboxylic acids or esters derived from said acids in which latter case ester interchange occurs and the esterifying radicals are replaced by polyether polyol radicals. The preferred polyether polyols are random and block copolymers of ethylene and propylene oxide of functionality fro~ 2 to 4, preferably, 2 to 3 and polytetramethylene glycol polymers of functionality greater than or equal to 2Ø
Generally speaking, the overall proportions of the components (i), (ii), and (iii) are such that the 37,052-F -12-active hydrogen-oontaining components (ii) and (iii) balance the isocyanate component (i) so that stoichio-metric equivalency of the rea~tants is maintained.
However, for various reasons, it is not always possible nor desirable to meet the 1:1 equivalency. Advanta-geously, the proportions are quch that the overall ratioof isocyanate groups to active hydrogen groups is in the range of from 0.90:1 to 1.10:1, preferably, from 0.95:1 to 1.05:1 and, more pre~erably, from 0.98:1 to 1.02:1.
It is frequently desirable, but not essential, to include a catalyst in the process. Any of the cata-lysts conventionally employed in the art to catalyze the reaction of an isocyanate with a reactive hydrogen--containing compound can be employed for this purpose;
see, for example, Saunders et al., Polyurethanes, Chemistry and Technology, Part I, Interscience, New York, 1963, pages 228-232; see also Britain et al., J. Applied Polymer Science, 4, 207-211, 1960. Such catalysts include organic and inorganic acid salts of, and organometallic derivatives of, bismuth, lead, tin, iron, antimony, uranium, cadmium, cobalt, thorium, aluminum, mercury, zinc, nickel cerium, molybdenum, vanadium, copper, manganese and zirconium, as well as phosphines and tertiary organic amines. Representative organotin catalysts are stannous octoate 7 stannous oleate, dibutyltin dioctoate and dibutyltin dilaurate.
Representative tertiary organic amine catalysts are triethylamine, triethylenediamine, N,N,N',N'--tetramethylethylenediamine, N,N,N',N'-tetraethyl-ethylenediamine, N-methylmorpholine, N-ethylmorpholine, N,N,N',N'-tetramethylguanidine, N,N,N',N'-tetramethyl--1,3-butanediamine, N,N-dimethylethanolamine and N~N--diethylethanolamine. The amount of catalyst employed 37,352-F -13-éj 7 is generally within the range of from 0.02 to 2.0 percent by weight based on the total weight of the reactants.
Included in the process is the one-shot procedure, wherein all the reactants are brou@h~L
together all at once in the extrusion apparatus, and the prepolymer or quasi-prepolymer techniques. The use of a prepolymer technique would, of course, be limited primarily to those formulations employing the polyol component (iii) wherein part or all of the polyol is first reacted with isocyanate and the isocyanate prepolymer, then fed to the extrusion apparatus along with the extender. However, the preferred method is the one-shot reaction.
Additionally, the process can also include various additives such as impact modifiers, fillers and fiber glass; antioxidants, pigments, fire retardants, plasticizers, reinforcing agents and W2X lubricants commonly employed in the art in such compositions.
These may be added along with the reactants or at a later stage through a downstream feed port, or at a post reactor compounding step.
The process in accordance with the present invention is carried out by feeding the above ingre-dients into a commercial multi-screw extruder which is, generally speaking, a twin-screw extruder. The screws can be co- or counter-rotating. Preferably, a co--rotating and self-cleaning twin-screw extruder is employed. The general procedures and extrusion equipmer.t described in U.SO Patents 3,642,964 and 3,963,67g can be employed herein except for the novel 37,052-F -14-¢; ~ ~
exceptions discussed hereinbelow. Generally speaking, the reactive extrusion process is carried out within an overall temperature ran~e of f~ " , 5aoc tG 280C. That is to say, individual zones may not all be at the same temperatures but their individual values will fall with n this range.
The reactants can be measured out using known means such as, for example, gear pumps, membrane or piston pumps for delivery to the extruder feed zone.
Figure 1 shows one schematic embodiment of the process wherein (A), (B), and (C) represent three separate reactant feed lines for the isocyanate component, polyol component~ and catalyst component respectively. It is not essential that all three lines be utilized. For example, catalyst may be included in the (B) feed line;
alternatively, and, if desired, the reactants may be mixed in a suitable mixing head before they are introduced into the extruder. In that case, (A) represents a mixing head which includes all the reactants with catalyst or else the catalyst may be added separately as (B). One of the advantages of the present process i5 that viscosity build-up of the reaction mixture in the FEED ZONE is not in any way a particular problem. In fact, one of the key features of the present process i3 that the reaction mixture viscosity should exceed 100,000 cps (~00 Pas) before reaching the critical SINGLE HIGH SHEAR MIXING ZONE
(hereinafter MIXING ZONE). In this regard, the gel time for the reactant systems should be less than about 10 seconds, preferably less than about 6 seconds and FEED
ZONE temperatures can fall wlthi~. a range of from 150C
to 250C. he FEED ZONE length and conveying screws are in no way critical to the present process and can be 37,052-F -15-2 ~
configured as in the previously mentioned U.S. patents.
Actual barrel lengths for the FEED ZONE will be defined by ~he overall L/D (lengt;l/diameter) of the ext~uder which will be discussed in detail below.
Besides the diff~rences in the reaction mix viscosities in the FEED ZONES between the present process and the prior art cited supra particularly U.S.
Patent 3,~63,679, the limitation o~ the present MIXING
ZONE to one single zone o~ high shear mixing is a very critical and novel ~eature which results in polymer improvements that otherwise cannot be obtained with the hard polyurethanes. Such multiple zones of high shear mixing are described in detail in the previously mentioned patents, particularly the '679 reference.
Generally speaking, such high shear mixing zones employ two series of broad edged multiple kneading elements or blocks mounted in intermeshing relationship on the pair of parallel mounted screws in the twin-screw extruder in each zone. The individual kneading elements or blocks can be triangular, circular or elliptical as typically disclosed in the figures 2 through 7 of the '679 patent.
The dimensions are such that there is minimal radial clearance between the inner surface of the barrel and the perimeter edges of the blocks. Hence, rotation of the screws subjects the reaction mixture to high shear force~. Additional mixing and application of high shear forces can be imparted, if desired, by mounting appropriate baffles but more usually reverse pitch kneading blocks. Generally speaking, conveying screws are present in the same extruder barrel sections which contain the zone of kneading blocks.
37,052-F -16-What distinguishes the present process is the fact that the high shear mixing is carried out in just a single ~ uf these multiple kneading elements and not a series of repetitive zones. Advantageously, the actual length of the kneading elements within the single zone will fall within a range of from 60 ~n. to 240 mm, preferably from 80 to 180, and more preferably from 120 to 180 mm.
In order to provide sufficient shearing forces in the polymer forming mixture, a sufficiently high shear rate or velocity gradient must be achieved.
Generally speaking, this is related to the combination of the minimal radial clearances between the barrel (extruder wall) and shearing edges of the blocks referred to above and the speed of screw rotation.
Advantageously, this clearance will fall within a range of from 0.05 nm to 0.6 mm, preferably from 0.1 to 0.4 mm. Screw rotation expressed in rotations per minute (r.p.m.) will fall within a range of from 140 to 500 r.p.m., preferably 150 to 300 r.p.m.
Temperatures in the MIXING ZONE will be controlled within a range similar to the FEED ZONE with optionally a slightly higher range, that is to say, from 150C to 280C. Capability of cooling this zone should be provided in the event that exotherm could exceed the upper limit of 280C.
The EXTRUSION ZONE, sometimes called the METERING ZONE, can be configured similarly to the prior art w th onl~ conveying screws. Temperatures are advantageously controlled to a range of from 180C to 280C. The reacted melt product is simply extruded at 37,052-F -17-the end through any desired molding tool or die known to the art such as, for example, slot dies, profile-forming ules and rods.
There is no particular limit on overall barrel ength other than what is dictated by practical con-siderations. However, a particularly attractive feature of the present process are the short barrel lengths which are possible. Advantageously, the L/D ratio can fall within a range of from 10/1 to 44/l, preferably from 15/1 to 25/1, most preferably from 15/l to 20/l.
Overall temperature control throughout the above L/D
ranges, whether it be through heating and/or cooling in particular zones, will fall within the previously stated range of from 150C to 280C. Overall residence times in the extruder when operating under these L/D, temperature, and r.p.m. conditions set forth above will fall within a range of from 5 to 45 seconds, preferably from 6 to 30 seconds, more preferably from 6 to 25 seconds.
The extruded polyurethanes can be in finally desired shape or else comminuted or pelletized for further molding or injection molding into desired article~. The polymers a3 obtained need no further treatment, havin~ attained their superior physical and mechanical properties as set forth in the three patents cited supra and already incorporated herein.
The following examples describe the manner and process of making and using the invention and set forth the best mode cor.templated by the inventors of carrying 37,052-F -18-_19_ out the invention but are not to be construed as limit-ing.
Exam~le 1 The following experiment sets forth a com-parison of two redc~ive extrusion methods, one in accordance with the invention (run 1) and the other (comparison 1? in accordance with the prior art.
A Werner and Pfleiderer ZSK-53 self-cleaning, co-rotating twin-screw extruder was fitted with five barrels of which four had high shear mixing zones. Each of the latter zones were 240 mm in length but only 120 mm of this length was formed of the actual high shear kneading blocks themselves with the remainder given over to conveying screws. Radial clearance between extruder wall and outer diameter of the shearing edges of each kneading block was about 0.2 mm. Screw speed was con-trolled to 460 r.p.m. Extruder temperatures were con-trolled by five independent barrel heating or cooling zones. Feed zone temperature was 225 + 5C, with extrusion zone being 215 ~ 5C and the intermediate zones including the four high shear mixing zones being 190 to 210C. ~ sheeting die, 200 mm width and 3 mm gap was flanged to the end of the extrusion zone.
For comparison 1, a mixture in the proportional pa~ts by weight of 100 part~ of 1,4-cyclohexanedi-3 methanol, 0.82 parts of trisnonylphenyl phosphite and0.69 parts of Irganox 1010 (antioxidant supplied by Ciba Geigy Corp.) was degassed and dehydrated under vacuum at 99C for 2 hours. Using a gear pump, this mixture was delivered to the front feed port of the extruder. This means that the length/diameter ~L/D) ratio for this feed 37,052-F -19_ passing through the 2344 mm of length for the five zones of the barrel was 44/1. A second gear pump delivered to ''-.e s~ e ront feed port 175.2 parts of~ melted 4,4'--methylenebis(phenyl isocyanate) per 100 parts of the above diol,-while a third pump delivered at the same proportional rate 0.33 part of a polyurethane catalyst Fomrez UL-22 which is dimethyltindidodecyl mercaptide supplied by Witco Corporation. Gel time of this reacting mixture determined by hand mixing the components rapidly in a beaker was less than 10 seconds.
The polymer was extruded onto a retal conveyor belt at 26C, cooled and diced. At this point the solidified polymer was observed for the formation of bubbles.
After drying at 115C in a dehumidifying hopper dryer with a dew point below -28C, the pellets were injection molded into test specimens. Their physical properties were determined according to ASTM test procedures with the results set forth in Table I.
Run 1 in accordance with the invention was carried out identically to the above comparison run in every respect except the reactant~ were fed into a downstream feed port. The second feed port was located in the extruder barrel which was just prior to the la~t (i.e. fourth) high shear mixing zone. Feeding the reactants at this point shortened the barrel to 919 mm and reduced the L/D to 17.3/1. More importantly, the reaction mixture passed through a single zone of high shear mixing wherein the actual length of kneading blocks was 120 mm.
Comp2riscn of the two extrudates showed run 1 to be essentially clear with the presence of very few minute bubbles, essentially no more than what are to be 37,052-F -20-2 ~
expected in the extrusion of transparent type thermo-plastics. Contrastingly~ Comparison 1 showed copious bubbles in the sol~dLl . Gd eAtrudate. In respect of color formation as measured by Yellowness Index, run 1 was much lower in color compared with comparison 1. As for molecular weights and other physical properties, ru~
1 appeared to be superior in most respects.
37,052-F -21-~ :?~
Run Comp. 1 Polymer M.W.l 232,432 286,654 5 Flex Modulus, psi ~- 103 (GPa) 311.3 (2.15) 305.0 (2.1) Flex strength, psi (MPa) 14,714 (101.4) 14,898 (102.7) Tensile strength, psi (MPa) Yield 11,624 (80.1) 11,634 (80.2) 10 8reak 8,634 (59.5) 9,086 (62.6) Tensile moduius, psi x 103 (GPa) 293.4 (2.02) 289.2 (1.99) Elongation (~) Yield 8.2 8.3 8reak 34.6 31.0 HDT2 ( C ) 66 psi (455 kPa) 133 135 264 psi (1820 kPa) 123 123 Notched Izod3 ft-lbs/in (J~m) notch 1/8" (3.175 mm) thick sample 1.10 (58.7) 1.24 (66.2) 1/4" (6.35 mm)thick sample 0.74 (39.5~ 1.40 (74.7) Yellowness IndeY4 3.05 5.75 ~ubble Formation5 copious very few bubbles bubbles Footnotes to TALLL I
-1 Polymer weight average molecular weight determined by gel permeation chromatography using a polystyrene reference as standard.
30 2 ~DT: Heat deflectiun temperature measured at the specified pressures in accordan~e with AST~ Test Method D-648.
3 Notched Izod: Izod impact strength measured on 1/8" and 1~4"
(3.175 mm and 6.35 mm) thick samples in accordance with ASTM
D256-56.
37, 052-F -22-r~
4 Yellowness Index: determined usinq ASTM D-1925 standard at a two degree observer angle using a Pacific Scientific Spectrogard Color Syste~, Silve~ Spring, Marylan~ 20910 with the illuminant being simul~ted average daylight.
5 Bubble Formation: refers to the qualitative visual observation of the extruded polymer for th~ formation o^ bubbles; presence of a very few minute b~bbles can be tole~ated ~Ind the polymers classified as essentially a ~lear plastic, ~hereas the formation of a copio~s number of bubbles is not accep`:able.
Example 2 Similarly to Example 1~ this experiment describes comparison 2 and run 2 reactive extrusions wherein the same apparatus and conditions were employed herein with the exception of different reactant com-ponents.
The mixture pumped to the first feed port for comparison 2 which ran through the four mixing zones was as follows: a degassed and dehydrated mixture of 100 parts of an 85/15 mole ratio of 1,4-cyclohexane-dimethanol and hydrogenated bisphenol-A, 0.77 parts trisnonylphenyl phosphite, and 0.64 parts of Irganox 1010; 158.35 parts of melted 4,4'-methylenebis(phenyl isocyanate); and 0.31 part of Fomrez UL-22. For run 2 which ran through only the ~ingle zone of high shear mixing, the same three part ingredient mixture was fed into the downstream feed port for the L/D ratio of 17.3i1.
The properties of the injection molded samples from the two runs are set forth in Table II. Signifi-c~rtly less gassing in the initial extrudate and lower color for molded run 2 specimens compared to comparison 37,052-F -23-2 0 ~ 7 ~
2 was observed. Their physical properties were essentially comparable.
Run Comp. 2 2 Polymer M.W. 203,761 212,193 Fles Modulus, psi x 103 (GPa) 320.6 (2.Zl) 311.6 (2.14) Flex strength, psi (MPa) 12,918 (89~ 12,812 (88) 10 Tensile strength, psi (MPa) Yield 11,887 (82) 11,825 (81.5) Break 8,729 (60.2) 8,664 (59.7) Tensile modulus, (psi x 103) 295.8 (2.04) 291.4 (2.01) Elongation (~) Yield 8.3 8.2 Break 22.1 24.9 ~DT (~C) 66 psi (455 kPa) 145 145 264 psi (1820 kPa) 135 139 Notched Izod ft-lbs/in (J/m) notch 1/8" (3.175 mm) thick sample 1.15 ~61.4) 1.02 (54.4) 1/4" (6.35 mm) thick sample 0.82 (43.8) 0.93 (49.6) 25 Yellowness Index 8.13 5.64 Subble Formation copious very few bubbles bubbles 3 Example 3 This experiment similar to those above compared the properties of the extrudates and the injection molded samples ~rom comparison 3 and run 3. Using the same extruder configurations and conditions set forth in 37,052-F -24-2 ~
Example 1, the comparison 3 ingredients were fed into the front feed port of the extruder barrel while the same ingredients were fed into tile uownsiream feed port for run 3 with the latter having only the single zone of high shear mixing. The ingredients were as follows:
degassed and dehydrated mixture of 100 parts of 1,6--hexanediol, 0.94 part trisnonylphenyl phosphite, and 0.78 part of Irganox 1010; 213.8 part of melted 4,4'--methylenebis(phenyl isocyanate); and 0.19 part of Fomrez UL-22.
The properties of the two product runs are set forth in Table III. The data show significantly less gassing and lower color for run 3 compared with its comparison sample.
3o 37,052-F -25-`2~
TABLE III
Run Comp. 3 3 -- , , .
PolymPr K.W. 583,000 642,500 5 Tensile strength, psi (MPa) Yield 8960 (61.8) 7650 (52.7) Break 6600 (45.5) 9865 (68) Tensile modulus, psi x 103 (GPa) 256 (1.77) 273 (1.88) Elongation (~) Yield 7 Break 27 166 HDT (C) 66 psi (455 kPa) 88 86 264 psi (1820 kPa) 75 76 Notched Izod ft-lbs~in (J/m) notch 1/8" (3.175 mm) thick sample 1.747 (93.3) 2.399 (128) 1/4" (6.35 mm) thi~k sample 1.294 (69.1) 1.782 (95.1) Bubble Formation COPIOUS VERY FEW
- BU~BLES ~UB8LES
EXample 4 This example describes the preparation of a hard thermoplastic polyurethane polymer in accordance with the present invention ~run 4) and comparison 4.
In run 4, a self-cleaning twin-screw Werner and Pfleiderer ZSK-120V was employed with a single zone of high shear mixing at an L/D ratio of 9.5/1 from the feed port and with an overall extruder L/D of 18.8/1. The actual length of kneading blocks in the high shear 37,052-F -26-mixing zone was 180 mm. Screw speed was 250 r.p.m. and with about 0.2 mm radial clearance between extruder wall and outei~ dia,l-eLe} of the shearing edges of each kneading block. Zone temperatures were feed, 188C;
mixing, 177 to 199C; and extrusion, 2300.
The reaction mixture ~hich was metered into the feed port in three streams in the following proportions in parts by weight was as follows: degassed and dehydrated mixture of 43.2 parts of 1,4-cyclohexane-dimethanol, 23.6 parts of 1,6-hexanediol 10.4 parts of a 650 molecular weight polytetramethylene glycol, 0.52 part of Irganox 1010, and 0.31 part of triphenyl phosphite; 130.79 parts of 4,4-methylenebis(phenyl isocyanate); and 0.10 part of a 50/50 weight mixture of stannous octoate and dioctyl phthalate. The extruded product was fed onto a cool conveyor as described in the previous examples and dicedO The extruded material was clear transparent with only a few minute bubbles being detectable. The injection molded product had the following properties set forth in Table IV.
Comparison 4 was carried out under essentially the same temperature conditions with identical ingredients to run 4 but using a twin-screw Werner and Pfleiderer extruder having an 83 mm diameter, equipped with three zones of high shear mixing and an L/D of 30~7/1.
3o A comparison of the two runs shows that run 4 provided a product with much superior molecular weight to the compar-son run ~ znd a measurably better yellow index and transmission. Notably, this was accomplished 37,052-F -27-20~ 9~rlJ7 with much less power consumption as compared with co~parison 4.
TABLE IV
Run Comp. 4 4 .
Polymer M.W. 266,302 359,352 Tensile Strength, psi (MPa) Yield 10,305 9,896 Break 7,867 7,703 Tensile Modulus, psi x 103 (GPa) 274 (1.89) 274.8 (1.9) Elongation (~) Yield 6.4 5.7 Break 42 45 Yellowness Index 5.52 4.74 Transmission at 380 NMl 58.05~ 61.97 Footnote to Table IV
1 Light transmittance in percent measured on injection molded disk measuring 2 inches (51 mm) diameter x 1/8" (3.2 mm) thick at 380 nanometers using Pacific Scientific Spectrogard Color Systems, Silver Spring, Maryland, 20910.
37, 052-F -28-
Claims (20)
PROPERTY OR PRIVILEGE IS CLAIMED ARE DEFINED AS FOLLOWS:
1. A reactive extrusion process for the continuous preparation of a polyurethane having a Tg greater than 80°C from a reaction mixture comprising a polyisocyanate and at least one polyol component by passing said reaction mixture through a twin-screw extruder having besides the feed zone, zones of high shear mixing and a metering zone, characterized by limiting the high shear mixing to a single zone.
2. A process according to Claim 1 wherein in said single zone of high shear mixing the radial clear-ance between the outer diameter of the shearing edges and the extruder wall is from 0.05 to 0.6 mm and the rotation of the screw is from 140 to 500 r.p.m.
3. A process according to Claim 1 wherein the reaction mixture is passed through said single zone of high shear mixing after having reached a viscosity greater than 100,000 cps (100 Pas).
37,052-F -29-
37,052-F -29-
4. A process according to Claim 1 wherein said reaction mixture comprises (i) an organic polyisocyanate, (ii) at least one chain extender, and (iii) 0 to 25 parts by weight per 100 parts of total polyurethane reactants of a polyol having a functionality of at least 2 and a molecular weight of at least 500.
5. A process according to Claim 1 wherein said polyurethane is a thermoplastic.
6. A process according to Claim 1 wherein said reaction mixture additionally comprises a urethane catalyst.
7. A process according to Claim 1 wherein the temperature of reactive extrusion is carried out at a temperature of from 150°C to 280°C.
8. A process according to Claim 1 wherein said polyisocyanate is selected from the group consisting of aromatic diisocyanates, cycloaliphatic diisocyanates, and mixtures thereof.
9. A process according to Claim 1 wherein said polyisocyanate comprises an aromatic diisocyanate.
10. A process according to Claim 4 wherein said extender comprises at least one diol having a molecular weight of from 60 to 400.
11. A process according to Claim 4 wherein said optional polyol has a functionality of from 2 to 3 and a molecular weight of from 500 to 6,000.
37,052-F -30-
37,052-F -30-
12. A process according to Claim 1 wherein the proportions of said polyisocyanate and at least one polyol are such that the ratio of equivalents of isocyanate to hydroxyl falls within a range of from 0.95 to 1.05.
13. A reactive extrusion process for the continuous preparation of a thermoplastic polyurethane having a Tg greater than 80°C which process comprises:
(A) adding to the feed zone of co-rotating twin-screw extruder a reaction mixture comprising:
(i) an aromatic diisocyanate;
(ii) at least one diol extender having a molecular weight of from 60 to 400;
(iii) 0 to 25 parts by weight per 100 parts of total polyurethane reactants of a polyol having a functionality of from 2 to 3 and a molecular weight from 500 to 6,000; and (iv) a urethane catalyst, wherein the proportions of said diisocyanate (i) and components (ii) and (iii) are such that the ratio of equivalents of isocyanate to hydroxyl is from 0.95 to 1.05;
(B) mixing and homogenizing said reaction mixture after having reached a viscosity greater than 100,000 cps (100 Pa-s) in a single zone of high shear mixing at a temperature of from 150°C to 280°C and wherein the radial clearance between the outer diameter of the shearing edges and the extruder wall is from 0.05 to 0.6 mm and the screw rotation is from 140 to 500 r.p.m.; and 37,052-F -31-(C) removing the resulting polyurethane via a metering and shaping zone.
(A) adding to the feed zone of co-rotating twin-screw extruder a reaction mixture comprising:
(i) an aromatic diisocyanate;
(ii) at least one diol extender having a molecular weight of from 60 to 400;
(iii) 0 to 25 parts by weight per 100 parts of total polyurethane reactants of a polyol having a functionality of from 2 to 3 and a molecular weight from 500 to 6,000; and (iv) a urethane catalyst, wherein the proportions of said diisocyanate (i) and components (ii) and (iii) are such that the ratio of equivalents of isocyanate to hydroxyl is from 0.95 to 1.05;
(B) mixing and homogenizing said reaction mixture after having reached a viscosity greater than 100,000 cps (100 Pa-s) in a single zone of high shear mixing at a temperature of from 150°C to 280°C and wherein the radial clearance between the outer diameter of the shearing edges and the extruder wall is from 0.05 to 0.6 mm and the screw rotation is from 140 to 500 r.p.m.; and 37,052-F -31-(C) removing the resulting polyurethane via a metering and shaping zone.
14. A process according to Claim 13 wherein said aromatic diisocyanate comprises 4,4'--methylenebis(pheryl isocyanate) and said polyol content (iii) is zero.
15. A process according to Claim 14 wherein said diol extender comprises 1,4-cyclohexanedimethanol.
16. A process according to Claim 14 wherein said diol extender comprises a mixture of 1,4--cyclohexanedimethanol and hydrogenated bisphenol-A.
17. A process according to Claim 14 wherein said diol extender comprises 1,6-hexanediol.
18. A process according to Claim 13 wherein said aromatic diisocyanate comprises 4,4'--methylenebis(phenyl isocyanate) and said polyol is present in the proportions of from 1 to 15 parts.
19. A process according to Claim 18 wherein said polyol has a molecular weight of from 650 to 2,000.
20. A process according to Claim 19 wherein said diol extender comprises a mixture of 1,4--cyclohexanedimethanol and 1,6-hexanediol and said polyol is a polytetramethylene glycol of molecular weight from 650 to 1,000.
37,052-F -32-
37,052-F -32-
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US37249889A | 1989-06-27 | 1989-06-27 | |
| US372,498 | 1989-06-27 |
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| CA2019877A1 true CA2019877A1 (en) | 1990-12-27 |
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ID=23468386
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002019877A Abandoned CA2019877A1 (en) | 1989-06-27 | 1990-06-26 | Melt polymerization process for making polyurethanes |
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| AU (1) | AU5949390A (en) |
| CA (1) | CA2019877A1 (en) |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5679756A (en) * | 1995-12-22 | 1997-10-21 | Optima Inc. | Optical thermoplastic thiourethane-urethane copolymers |
| CN102719901A (en) * | 2012-06-28 | 2012-10-10 | 东华大学 | Polyester spinning method of reducing screw melt extrusion machine |
Families Citing this family (20)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4948859A (en) * | 1988-10-28 | 1990-08-14 | Minnesota Mining And Manufacturing Company | Extruder polymerization of polyurethanes |
| KR960011003B1 (en) * | 1991-06-19 | 1996-08-16 | 미쯔이 도오아쯔 가가쿠 가부시기가이샤 | Method of urethanating reaction |
| CN1059478C (en) * | 1994-03-12 | 2000-12-13 | 陶宇 | Method for producing polyurethane elastic fiber |
| DE4437586A1 (en) | 1994-10-20 | 1996-04-25 | Basf Schwarzheide Gmbh | Process for the preparation of thermoplastic polyurethanes |
| CN101111353B (en) | 2004-06-24 | 2011-09-28 | 世纪-博得美国公司 | Continuous forming apparatus for molding three-dimensional foam products |
| DE102005004967A1 (en) * | 2005-02-03 | 2006-08-10 | Basf Ag | Process for the continuous production of thermoplastically processable polyurethane elastomers |
| CA2646735A1 (en) | 2006-03-24 | 2007-10-04 | Century-Board Usa, Llc | Extrusion of polyurethane composite materials |
| CA2710918C (en) * | 2007-12-28 | 2017-02-14 | Bostik, Inc. | A continuous process for the production of moisture-cure, polyurethane sealants and adhesives |
| FR2929612B1 (en) * | 2008-04-03 | 2011-02-04 | Rhodia Operations | METHOD FOR OLIGOMERIZING CONTINUOUS ISOCYANATES |
| EP2294105B1 (en) | 2008-05-23 | 2018-07-11 | Lubrizol Advanced Materials, Inc. | Fiber reinforced tpu composites |
| US9481759B2 (en) | 2009-08-14 | 2016-11-01 | Boral Ip Holdings Llc | Polyurethanes derived from highly reactive reactants and coal ash |
| US8846776B2 (en) | 2009-08-14 | 2014-09-30 | Boral Ip Holdings Llc | Filled polyurethane composites and methods of making same |
| US8501066B2 (en) * | 2010-10-01 | 2013-08-06 | A. Raybond Et Cie | System and method for manufacturing heat-activable adhesive pellets |
| EP2763847A4 (en) | 2011-10-07 | 2015-08-19 | Boral Ip Holdings Australia Pty Ltd | Inorganic polymer/organic polymer composites and methods of making same |
| TWI667285B (en) | 2013-10-18 | 2019-08-01 | 德商巴斯夫歐洲公司 | Production of expanded thermoplastic elastomer |
| US10138341B2 (en) | 2014-07-28 | 2018-11-27 | Boral Ip Holdings (Australia) Pty Limited | Use of evaporative coolants to manufacture filled polyurethane composites |
| US9752015B2 (en) | 2014-08-05 | 2017-09-05 | Boral Ip Holdings (Australia) Pty Limited | Filled polymeric composites including short length fibers |
| WO2016118141A1 (en) | 2015-01-22 | 2016-07-28 | Boral Ip Holdings (Australia) Pty Limited | Highly filled polyurethane composites |
| US10030126B2 (en) | 2015-06-05 | 2018-07-24 | Boral Ip Holdings (Australia) Pty Limited | Filled polyurethane composites with lightweight fillers |
| WO2017082914A1 (en) | 2015-11-12 | 2017-05-18 | Boral Ip Holdings (Australia) Pty Limited | Filled polyurethane composites with size-graded fillers |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR956605A (en) * | 1943-07-24 | 1950-02-02 | ||
| BE759829A (en) * | 1969-12-03 | 1971-06-03 | Upjohn Co | PREPARATION OF POLYURETHANES |
| US3963679A (en) * | 1973-01-19 | 1976-06-15 | Bayer Aktiengesellschaft | Process for the production of polyurethane elastomers |
| DE2447368A1 (en) * | 1974-10-04 | 1976-04-08 | Basf Ag | Thermoplastic polyurethane elastomers prepn. - by introducing components into extruder inlet zone, and maintaining definite temp. profile in extruder |
| IT1196527B (en) * | 1986-07-21 | 1988-11-16 | Ausimont Spa | PROCEDURE FOR THE PREPARATION OF THERMOPLASTIC POLYURETHANE |
| US4822827A (en) * | 1987-12-17 | 1989-04-18 | The Dow Chemical Company | Thermoplastic polyurethanes with high glass transition temperatures |
-
1990
- 1990-05-14 AU AU59493/90A patent/AU5949390A/en not_active Abandoned
- 1990-05-14 WO PCT/US1990/002869 patent/WO1991000304A1/en unknown
- 1990-06-26 CA CA002019877A patent/CA2019877A1/en not_active Abandoned
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5679756A (en) * | 1995-12-22 | 1997-10-21 | Optima Inc. | Optical thermoplastic thiourethane-urethane copolymers |
| CN102719901A (en) * | 2012-06-28 | 2012-10-10 | 东华大学 | Polyester spinning method of reducing screw melt extrusion machine |
Also Published As
| Publication number | Publication date |
|---|---|
| WO1991000304A1 (en) | 1991-01-10 |
| AU5949390A (en) | 1991-01-17 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FZDE | Discontinued | ||
| FZDE | Discontinued |
Effective date: 19941226 |
|
| FZDE | Discontinued |
Effective date: 19941226 |