CA2105468A1 - Compounds with liquid crystalline properties and coating binders based thereon - Google Patents

Abstract

Polymeric vehicles with liquid crystalline-like properties, solvent dispersible polymeric vehicles, formulated coating compositions with liquid crystalline-like properties and a method for imparting liquid crystalline properties to a coating binder are described. The materials with liquid crystalline-like properties lack structural segments previously regarded as mesogenic.

Description

WO92/16588 ~ PCT/US92/0215~

COMPO~ND8 ~ITH LIO~ID ÇRY8T~L~INE
PROPERTI~8 XND COATING BIND~R8 ~A8ED THBR~ON

This application relates to compounds with liquid crystalline (LC)-like properties and polymeric vehicles for coatings binders which include such LC-like compounds. More particularly, this application relates to compounds with LC-like properties wherein parts or sections of the compounds lacX structural segments previously regarded as mesogenic. The structural segments of the compounds of the invention, however, provide certain properties that are similar to mesophases, but surprisingly these structures have heretofore not been identified as mesogens.

BACRGRO~ND
The properties of liquid crystalline (LC)-polymers differ from those of amorphous or crystalline polymers in ways that often have commercial value.
Heretofore, the term "mesomorphous" has been synonymous with "liquid crystalline". LC polymers are known to form mesophases having order intermediate between crystalline polymers and amorphous polymers. See Flory, P.J., Advances in Poivmer Science. Liquid Crvstal Polvmers I;
Springer-Verlag; New York (1984) Volume 59; Schwarz, J.
Mackromol, Chem. Rapid Commun. ~1986) 7, 21. Further, mesophases are well known to impart strength, toughness and thermal stability to plastics and fibers as described by Kwolek et al. in Macromolecules (1977) 10, 1390: and by Dobb et al., Advances in Polymer Science. Lisuid Crvstal_Poly~ers II/III (1986) 255(4), 179. Very recently it has been recognized that polymeric networks made by cross-linking LC polymers and oligomers also have greatly enhanced properties.

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W092/16588 PCT/US92/021~5 -Because of their inherent scientific interest and of their many actual and potential commercial applications, LC polymers have been extensively studied.
Many published studies have focused on identifying and classifying the kinds of chemical structures that are associated with liquid crystallinity in polymers. These studies have led to formulation of a principle, which has been generally accepted: that liquid crystallinity in polymers is invariably associated with the presence of "mesogenic groups". Mesogenic groups are chemical structures within the polymer which are capable, in certain circumstances, of imparting liquid crystallinity.
Lengthy review articles cataloging and classifying mesogenic groups have been written. Most commonly, mesogenic groups are chemical structures that contain a rigid sequence of at least two aromatic rings connected in the para position by a covalent bond or by rigid or semi-rigid chemical linkages. Optionally, one of the rigid aromatic rings may be naphthalenic rings linked at the 1,5- or 2,6- positions. Of several broad classes of mesogenic groups, the most common contains two or more 1,4-arylene (or, less commonly, 1,4-trans-cyclohexenyl) rings covalently connected by rigid or semi-rigid linkages which include but are not limited to 1l 1l X = - O - C -, - C - O -, -CH = N -, - O-CH2 -, - C = N -W092tl6588 .` ~ PCT/US92/02155 > C = C / ---- C>

Il o O O O O
_o~ -O-, ~ O~- O- 11-and various mesogens described in Ober et al., Liouid Crvstal Polvmers with Flexible SDacers in the Main Chain, Advances in ~olvmer Science 59, 104 at 105-117 which is incorporated by reference herein.
Until recently the study of LC polymers as potential coatings binders has received little attention.
Chen et al., J. Coat. Technol. 1988, Vol. 60 (756), p. 39 prepared al~yd resins with mesogenic poly p-hydroxybenzoic (PHBA) acid segments (a common LC monomer) pendant to the polymer backbone. Improved dry times and film properties were observed for the alkyds. Chen et al., J. A~pl. Polvm.
Sci. 1988, Vol. 36, p. 141 also prepared LC acrylic polymers with pendant poly PHBA groups that gave excellent lacquer and enamel properties. Wan~ et al., ~lYm. Mater. Sci. Ena.
1987, 56, 645, prepared oligoester diols which were end-capped with PH8A units. Cross-linked enamels were prepared that displayed excellent properties. Dimian et al., Polvm. Mater. Sci. Ena. 1987, 56, 640, synthesized LC
oligomer diols based on the mesogen 4,4'-terephthaloydioxydibenzoyl chlo:ride. The LC diols were cross-linked to give ~namels with excellent properties.

wo92/t6s88 PCT/US92/02155 Japanese patents have claimed that PHBA enhances the properties of polyester powder coatings; Japanese Kokai 75/40l 629 (1975) to Maruyama et al.; Japanese Kokai 76/56/839 (1976) to Nakamura et al.; Japanese Rokai 76/44,130 (1976) to Nogami et al.; and Japanese Kokai 77/73,929 (197?) to Nogami et al.
In classifying "mesogenic groups" one also, overtly or by implication, classifies other groups as "non-mesogenic". Such groups are chemical structures that are outside the boundaries of the various types of mesogenic groups. They are generally considered incapable of imparting liquid crystallinity under any circumstances. Two types of non-mesogenic groups are of particular interest:
(1) single 1,4-arylene units that are connected to other aromatic rings in the polymer structure by flexible rather than rigid or semi-rigid linkages and (2) 1,3-arylene rings connected in any way. Examples type of (1) and groups derived from terephthalic acid, hydroquinone and 4-hydroxybenzoic acid are:
CO~H OH COOH
l I

COOH OH OH
Examples of non-mesogenic groups of type (2) are those derived from isophthalic acid, resorcinol and 3-hydroxybenzoic acid:

WO92/16~88 ~iU`;~& ~ PCT/US92/0215 COOH OH COOH

COOH OH OH

In a recent publication tKricheldor, Pakull and Buchner, Macromolecules 21, 1929-1935 (1988)] it was reported that a polymer containing two electronically different aromatic non-mesogenic groups is 'lliquid crystalline". The structure of this polymer is:
O O O

o~ ( N~ 2)~ _ C- 0~+ (1) n Krichedor et al. considered their f inding very surprising. They explained the formation of liquid crystallinity by postulating a "special co-operative effect, presumably a charge-transfer interaction, between the aromatic monomer units." They stated "...the mesophase of 4e (the above Formula 1) is formed despite the absence of mesogenic groups. Obviously, special interaction between the bisphenol and the benzophenone imide unit is responsible for the observed smectic phases. This interaction is most likely a weak charge-transfer (CT) complexation." It was taken as a given that the isolated bisphenol unit is not a mesogenic WOQ2/16588 8 PCT/US92/0215~ _ group which may be a matter of semantics when the resulting compound exhibits LC-like properties. Indeed, semantically because the resulting compounds have LC-like properties certain linkages or parts of the compounds may be considered mesogens or mesogenic.
In another publication ~Bilibin, et al.
Makromol. ,Chem.. Ra~id Commun. 6, 209-213 (1985)] it was reported that chemical compounds of the structure O

H~OC ~ O-- C-- (CH2)n -- C-- O ~ C0011 n = 6, 7, 8 "....exhibit monotropic mesomorphism. This can be accounted for by intermolecular hydrogen bonding as in the case of the 4-alkoxybenzoic acid melt." Also see Fornasier et al. Liquid Crystals 8, 787-796 (1990).
It is an ob~ect of this invention to provide polymeric vehicles for coatings binders which have LC-like properties.
It is another object of this invention to provide a method of imparting LC-like properties to coatings binders.
It is still another ob;ect of this invention to provide solvent dispersible polymeric vehicles for coatings binders which have LC-like properties.
It is yet another object of the invention to provide a method which provides polymeric vehicles with new thixotropic and anti-sagging properties.
Still further objects and advantages of the invPntion will be found by reference to the following description.

WO 92/16!;88 ~ g PCr/VS92/0215 8VMMARY OF THE IN~NTION
In this invention new polymeric vehicles with LC-like properties, solvent dispersible polymeric vehicles and formulated coating compositions with LC-like S properties and a method for imparting liquid crystal-like properties to a coating binder and a method for providing a polymeric vehicle with thixotropic and anti-sagging properties have been discovered. The method and new polymeric vehicles of the invention provide coating binders with LC-like properties; and as a result, the method and polymeric vehicle of the invention provide coating binders and coatings with improved properties including hardness and impact resistance heretofore generally associated with known mesogenic groups and known LC polymers in the polymeric vehicle.
When applied to a substrate, some of the polymeric vehicles of the invention having LC-like properties, provide coating binders having a pencil hardness of at least about 3H and a reverse impact resistance of at least about 60 inch-lbs. at a binder thickness of about 1 mil. In one aspect of the invention, the polymeric vehicle comprises a dispersible polyester having the general Formula I shown below or dispersible adducts of the polyester having the general formula shown below:
I. HO-V-Al'-(W-Ar-X-Al-Y)_ -Ar'-Z-OH
- m wherein o V= -C- or a covalent bond;
Al' = (CH2)n or a covalent bond;
O O
W= -CO-, -OC- or a covalent bond;

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WO92/16~88 PCT/US92/0215 Ar = ~ , or O O
Il 11 X - -C0- or -OC-Al = (CH2) n Il 11 Y = - C0- , -OC- or a covalent bond, ll but if X = -0-C- and if V = bond, and if Al' = bond, and if W = bond and if z s bond, then Y =
ll 15 ~CO~;

Ar' _ ~ or a c~v~l~nt ~ond; cnd Z = -C- or a covalent bond wherein ~= l to 20, but when V - bond, Al' J bond, W ~ bond and Z ~ bond, ~ > 2 n = 2 to 20.
As used herein the term ~dispersible" maans that the polyester of the general formula or the adducts (amine salts or mono-oxirane addition products) of that polyester are dispersible in a medium at 25 C. which medium may also include a dispersant. The medium for the dispersion may be water, organic solvent, cross-linking agent, reactive diluent and ~ay be or include the adducts of the polyester of general Formula I. The adducts of WO92/16~88 ~i~v~ ) PCT/US92/0215 the polyester of Formula I also may act as a dispersant as well as serve as the medium. While the term "polyester" is used in connection with the compounds of the general formula, the compounds defined by the above general formula have molecular weights of less than about lO,000, and as a result, are oligomers.
In another aspect of the invention, the polymeric vehicle of the invention comprises adducts of the hydroxyl or carboxyl terminated polyester with the above general formula and a cross-linking agent in an amount effective for cross-linking the polyester to provide the coating binder. Many of polyesters which form part of the polymeric vehicle of the invention are not dispersible in solvents com~only used in connection with coatings. When there is a predominately aqueous media, to achieve solvent dispersibility, polymers which form a part of the polymeric vehicle of the invention are made water reducible by converting the polymers into salts (such as amine salts) by reacting a base (such as an amine) with the polyesters having acid functionality.
In this aspect of the invention, a polyester having the above general formula which is a diol is converted into a diacid, tri or tetracid with a polyfunctional acid or anhydride thereof having from 4 to 20 carbon atoms. This conversion provides a carboxylated polyester or a partly carboxylated polyester where all of the hydroxy groups on the polyester have not been reacted with an acid or anhydride. In this aspect of the invention, the polyester of the general formula is reacted with at least about lO percent and preferably 25 percent of the stoichiometric amount of acid or anhydride required to carboxylate all of the hydroxyls of the diol polyester of 5eneral formula to provide a carboxylated polyester, When the carboxylated polyester is combined with ~ base, WO92/16~88 PCT/US92/02155 _ such as an amine, it forms a water dispersible salt.
This provides water dispersibility of the polyester and polymeric vehicle of the invention. Preferably the base has a boiling point of less than about 200-C.
In another aspect of the invention, dispersi-bility of the polymeric vehicle of the invention in organic solvents is effected (l) by grafting a mono-oxirane having not more than 2S carbon atoms onto the polyester of the above general formula to provide a modified polyester which is dispersible in organic solvents in a non-aqueous media or (2) by dispersing the polyester of the above general formula in a reactive diluent in combination with the organic solvent. Broadly the reactive diluent is a hydrocarbon organic liquid having from about 2 to about 5, prefer~bly 2, functional groups such as carboxyl and hydroxyl, preferably hydroxyl. Through its functional groups, the reactive diluent is capable of reacting with the cross-linking agents described herein (preferably an aminoplast or polyisocyanate) and has a viscosity at 25-C. of from about 0.5 Pa-s to about 25 Pa-s. By way of example, the reactive diluents may be a reaction product of (l) an aromatic hydroxy acid or diacid such as terephthalic acid, para hydroxy benzoic acid or 2,6-naphthalenic acid with a mono-oxirane having not more than 25 carbon atoms such as the oxiranes described in connection with making a modified polyester by grafting a mono-oxirane thereon or (2) is the reaction product of a straight chain aliphatic diacid having 4 to 14 carbon atoms with the cyclohexyl diol l,4-dimethylol cyclohexane which has the str~cture ~2 C~ C~2~ or is the reaction product of l,6-cyclohexane d ~ rboxylic acid with a straight chain diol having 4 to 14 carbon atoms.

W092/16588 ~l'J~ PCT/US92/02155 In the aspect of the invention which includes grafting the mono-oxirane onto the polyester to provide a modified polyester, the modified polyester is the reaction product of the mono-oxirane, the mono-oxirane S being in an amount effective for making the polyester dispersible in an organic solvent. In this aspect of the invention, if the polyester of the general formula is a polyol such as diol, that diol first is reacted with a polyfunctional carboxylic acid or anhydride, having from about 4 to 20 carbon atoms as described above, to car-boxylate the diol polyester (and make it a carboxylated polyester) prior to reacting the polyester with the oxirane to graft it onto the polyester. The modified polyester with the oxirane grafted thereon may be dispersed into an organic solvent medium by itself or as a part of a blend of modified polyester and polyester of the general formula. The modified polyester in the blend is in an amount effective for making the blend dispersible in an organic solvent which amount is a function of the solvent and the amount of oxirane grafted onto the polyester. In general for a polyester which has been reacted with a stoichiometric amount of oxirane, the blend of polyester and modified polyester will include at least about 70 weight percent and preferably at least about 80 weight percent modified polyester in dispersions having at least about 50 weight percent polyesters tboth modified and unmodified polyester).
In the aspect of the invention which uses the reactive diluen~ As opposed to the modified polyester, the reactive diluent ~ay be used to disperse carboxylic polyesters without hydroxy groups, but hydroxy polyesters are preferred. In addition to ~sing organic solvents as the media for such dispersion, the reactive diluent may be used as a part of the ~edia or function as a disper-w g~
0 92tl658 PC~r/US92/021~5 6ant in such dispersions. Stable nonagueous dispersions of hydroxy polyesters, such as diol polyesters of the general formula are formed at polyester to diluent ratios of from about 10:1 to about 1:4 and preferably from about 4:1 to about 1:4 at solids levels of from about 40 to about 80 weight percent. These dispersions provide a formulated coating composition which includes the polyester of the general formula, cross-linking agent, reactive diluent, and in and a preferred aspect a second dispersant additional to the reactive diluent and optionally organic solvent as an additional medium.
While not intending to be bound by any theory, in the aspect of the invention which includes the reactive diluent with the polymeric vehicle in a nonaqueous media, it is believed that sometimes the reactive diluent associates with both the polyester of the general formula and solvent. This association coupled with the bulky structure of the reactive diluent results in steric stabilization. Additionally, the reactive diluent is di-or polyfunctional which functionality allowscross-linking by polyisocyanate and melamine resins during the curing of the polymeric vehicle into a coating binder.
Without using polyesters with mesogens or groups thought to be mesogenic, the invention also provides a method of imp~rting liquid crystalline properties to a coating binder with resulting, in certain cases, improved hardness and impact resistance associated with liquid crystalline polymeric vehicles. This method includes mixing a polyester without mesogens or groups which impart L/C properties, a modified polyester or adducts of the polyester of the general formula with a cross-linking agent to provide, in some cases, a pol~meric vehicle or a formulated coating composition which will provide~a WO92/16~88 ~ PCT/VS92/02155 resulting coating binder having a pencil hardness of at least 3H and a reverse impact resistance of at least about 60 inch-lbs. at a binder thickness of about 1 mil.
The invention provides polymeric vehicles and formulated coating compositions with ~Inon Newtonian"
viscosities and rheological properties which are well suited for polymeric vehicles for paint coatings. The invention provides compositions which have high vis-cosities at low shear rates, viscosities of at least lo about 15 Pa-s at shear rates of not greater than 1,000 sec1 in the temperature range of from about 25-C. to about 60 C., but low viscosities at high shear rates, viscosities of not greater than 5 Pa-s at shear rates of at least about 3,000 sec~1 in the temperature range of from about 25 C to about 60-C. Moreover, the invention proYides polymeric vehicles and formulated coating compo-sitions which have a viscosity which increases when the temperature of the polymeric vehicle is raised such as raised above about 25 C for curing. Such properties are well suited for polymeric vehicles for coating binders for paint. Low viscosities at high shear rates provide a coating composition which can be readily applied by means which provide for high shear rates: spraying, rolling or brushing. Moreover, the invention provides for the design of polymeric vehicles and formulated coating com-positions which thicken and increase in viscosity at critical bake or cure temperatures as the polymeric vehicle is heated above 25-C. This avoids oven sagging of the coating composition during curing at temperatures higher than ambient. Oven sagging is a common problem for many enamels due to a dramatic drop in viscosity at higher temperatures. The invention provides a polymeric vehicle which has a viscosity which increases with temperature in certain temperatures ranges until a~

wo 92/l63~l V a ;~ ~ ~ PCT/US92/02155 maximum; as a result, the viscosity is sufficiently high at baking temperatures to minimize sagging.
Besides the latter special viscosity-vs-temper-ature behavior, the polymeric vehicles of the invention are thixotropic as well as shear thinning and exhibit yield stress below a certain temperature (such as T~TC).
While thixotropic compositions are not new, the extent of "shear thinning" permitted by the invention in polymeric vehicles of the invention is novel and has not been heretofore observed in polymeric vehicles comprising oligomeric mixtures which are substantially free of polymers having molecular weights greater than about 10,000. The thixotropic and yield-stress properties of the polymeric vehicles of the invention enhance the anti-sagging properties of the formulated coatings of theinvention, since they will allow lower viscosity at application conditions (such as brushing, rolling, and spraying) while remaining at a higher viscosity at baking condition (without pre-shearing or at lower shearing force). While higher viscosity during c~ring is good for anti-sagging, it may lead to poor levelling. Thus, an intermediate viscosity should be chosen for formulated coating compositions in order to obtain both good levelling and sagging resistance. This can be achieved by adjusting the curing temperature or the type and amount of solvent around the viscosity maximum.
The polyester of the invention is the reaction product of an aromatic compound selected from the group consisting of (I) a 1,4-disubstituted benzene which has hydroxyl or carboxylic su~stitution such as terephthalic acid, hydroquinone, (II) a 2,6-disubstituted naphthalene which has hydroxyl or carboxylic substitution, such as

2,~-dihydroxy- or dicarboxy naphthalene, and (III) mixtures thereof with a linear diacid or diol having 6 to Wo92/16588 ~1 ~J-t 6 ') PCT/US92/02155 17 carbons ~nd 4 to ~5 ~et~ylene groups. The l$n~arity of the ~cid or diol co-reactant provides flexible ~pacer groups between aromatic groups; yet, surprisingly, the polymeric vehicle of the invention has LC-like properties.
D~BC~IPTIO~ OF T~IE PEUS~E~D EMBODI~
The polyesters of Formul~ I a8 a part of ~
dispersible polymeric vehicle,including but not llmited to being dispersible in ~n ~gueous or or~nic solvent lo media, ~mino calt adducts thereof, oxirane adducts of the hydroxyl and carboxyl terminated polyester of Formula I
and blends according to the $nvention may be used to ma~e a polymeric vehicle or a formulated coating for a coating binder for improved properties such as would be expected in polymeric vehlcles wlth known mesogenic groups. In certain aspects of the invention, some of the polymeric vehicles of the in~ention provide coating binders having a pencil hardness at least about 3H ~nd a reverse ~mpact resistance of at least about 60 inch-lbs. at a binder t~ickness of about 1 mil.
The polymeric vehicle of the invention includes cross-linking ~gents which react with the polyester of the general Formula I, ~mine ~alts thereof or oxlrane adducts of carboxyl or hydroxyl terminated polyesters of Formula I to prov$de a coatlng binder wh$c~ ~as ~ reverse impact resistance of at le~t ~bout 60 lnch-lbs. and a pencil hardnes~ of at least about 3H. The cro~-linXing ~ent ~as ~ functional$ty oS two or ~ore, t~at 1~, it contains at le~st two and prefsrably three or ~ore reactive groups: ~xa~ples ~re polycarboxylic acids, polyol~, ~m$nopl~st ro~in~, poly$60cyanate resins ~uch as the trlmer of tolu~n~dil~ocyanate, ~examet~ylene d~i~ocyanate (X~DI) and ~ biurct ther~of, isop~rone diisocyanate (IPDI), i~ocyanates and ~$xtures thereof.

WO92/1658~ PCT/US92/021 The aminoplast resin may be a melamine resin, such as hexakis (methyloxymethyl) melamine resin (HMMM). The polyisocyanate resin may be a blocked polyisocyanate resin which is blocked with active hydrogen compounds such as alcohols, phenols, oximes or lactams.
Solvents and known additives such as pigments may be added to the polymeric vehicle to provide a formulated coating composition which is a dispersion. In the aspect of the invention which provides a polymeric vehicle for a coating binder, the coating binder gives a coating film with high hardness, flexibility, and impact resistance heretofore associated only with polymeric vehicles which include known mesogens. After the formu-lated coating is applied to a base or substrate, solvents (if present) evaporate leaving a solvent-free film.
Evaporation and cross-linking may be accelerated by heating, as by baking. An improved film provided by the polymeric vehicle with improved hardness, flexibility and impact resistance, and the coating binder therefor, are a particularly important part of this invention. Moreover, an important aspect of this invention is that the raw materials for the polymeric vehicle are inexpensive and readily available. Since the coating binder primarily provides the desired film characteristics, the properties of the coating binder are particularly described primari-ly by tests which measure hardness and impact resistance.
Definition~
As used in this application, "polymer" means a polymer with repeating monomeric units as defined by the gen~ral formula and includes oligomers as defined herein.

~Polyester" means a polymer which has C0 linkages in the main chain of the polymer. "Oligomer" means a compound that is a polymer, but ~as a number average weigh~ not ~V092/16~88 ~ g PCT/US92/0215 greater than about lO,000 with repeating monomeric units.
"Adduct of the polyester" means the following c~emical addition products of the polyester of the general formula I: (l) the amine salt of acid polyester of general S Formula I or of the carboxylated hydroxyl terminated polyester of general Formula I; and (2) a mono-oxirane bonded onto the polyester of the general Formula I or onto the carboxylated hydroxyl terminated polyester of general Formula I. "Cross-linking agent" means a di- or polyfunctional substance containing functional groups that are capable of forming covalent bonds with hydroxyl and carboxyl groups that are present on the polymer;
aminoplast and polyisocyanate resins are members of this class; melamine resins are a sub-class of aminoplast resins. "Modified polyester" means a polyester having covalently bound modifying mono-oxirane groups as described herein and the term "grafted" or "grafting"
used herein in connection with mono-oxiranes means that such oxiranes are covalently bound to the polyester; that is, the oxirane adduct is made in a process of adding the oxirane to an existing polyester. "Polymeric vehicle"
means all polymeric and resinous components in the formu-lated coating, i.e., before film formation, including but not limited to modified polymers. The polymeric vehicle may include a cross-linking agent and reactive diluent as described herein. "Coating binder" means the polymeric part of the film of the coating after solvent has evapor-ated and after cross-linking. "Formulated coating" means the polymeric vehicle and solvents, pigments, catalysts and additives which may cptionally be added to impart desirable application characteristics to the formulated coating and desirable properties such as opacity and color to the film.
"Solvent" means water and/or an organic solvent.

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WO92/16588 PCT/US92/0215~ -"Organic solvent" means a liquid which includes but is not limited to carbon and hydrogen which liquid has a boiling point in the range of from about 35 C. to about 300-C. at about one atmosphere pressure.
"VOC" means volatile organic compounds and "low VOC" means about 1 pound per gallon or about 120 grams of volatile organic compounds per liter of formulated coat-ing composition, not including water. "Volatile organic compounds" are defined by the U.S. Environmental Protec-tion Agency as any organic compound which participates in atmospheric photochemical reactions, except for specific designated compounds which have negligible photochemical activity. Water and C02 are not VOCs. VOCs have been generally designated to include but are not limited to myrcene, cumene, butyne, formaldehyde, carbon tetra-chloride, aniline, dimethylnitrosamine, formic acid, acetone, chloroform, hexachloroethane, benzene, tri-chloroethane, methane, bromoethane, ethane, ethene, acetylene, chloromethane, iodomethane, dibromomethane, propane, l-propyne, chloroethane, vinyl chloride, acetonitrile, acetaldehyde, ~ethylene chloride, carbon disulfide, thiobismethane, bromoform, bromodi-chloromethane, 2-methylpropane, l,l-dichloroethane, 1,1-dichloroethene, phosgene, chlorodifluoromethane, trichlorofluoromethane, dichlorodifluoromethane, tetrafluoromethane, tetramethylplumbane, 2,2-dimethyl-butane, monomethylester-sulphuric acid, dimethyl-butanone, pentachloroethane, trichloro-trifluroethane, dichlorotetrafluoroethane, hexachlorocyclopentadiene, dimethyl sulfate, tetraethylplumbane, 1,2-dibromopropane, 2-methylbutane, 2-methyl-1,3-butadiene, 1,2-dichloro-propane, methyl ethyl ketone, 1,1,2-trichloro ethane, trichloroethene, 2,3-dimethylbutane, tetrachloroethane, dimethyl-3-methylene-bicyclo-heptane, A-pinene, WO92/16588 PCT/US92~0215 hexachlor~-butadiene, methylnaphthalene, naphthalene, quinoline, methylnaphthalene, phenyl-propanone, dimethylbenzene, O-cresol, chloro-methylbenzene, dichlorobenzene, trimethylbenzene, tetramethylbenzene, dibromo-3-chloropropane, 3-methylpentane, 3-pentanone, methylcyclopentane, (l-methylethyl)-benzene, l-(methyl-ethenyl)-benzene, l-phenylethanone, nitrobenzene, methyl-methylethyl-benzene, ethylbenzene, ethenylbenzene, benzychloride, benzonitrile, benzaldehyde, propylbenzene, butylbenzene, 1,4-diethylbenzene, 2,4-dimethylphenol, dimethylbenzene, chloro-methylbenzene, dichlorobenzene, dibromoethane, 3-bromo-1-propene, butane, l-butene, 1,3-butadiene, 2-propenal, bromochloroethane, 1,2-dichloroethane, propanenitrile, 2-propenenitrile, 2-methylpentane, 2-pentanone, 2,4-dimethylpentane, 1,3-dimethylbenzene, m-cresol, 2,4-dimethylpyridine, 2,6-dimethylpyridine, trimethylbenzene, dimethylphenol, trichloro-benzene, trimethyl-pyridine, bromobenzene, methylcyclohexane, toluene, chlorobenzene, phenol, 2-methylpyridine, pentene, 2-pentane, bromo-chloro-propane, lH-pyrrole, tetrahydrofuran, hexane, 1,4-dichlorobutane, cyclohexane, cyclohexene, pyridine, octaine, 1-octene, nonane, dodecane, propene, 2-methyl-1-pentene, 2-methyl-1-propene, isoquinoline, trichlorobenzene, propanal, butanal, 1,4-(dioxane), l-nonene, decane, dibromochloromethane, 2-chloro-buradiene, tetrachloroethene, dimethyl-met~ylene-bicyclo-heptane, 1,2-diethylbenzene, (l-methyl-propyl)-benzene, Acetic Acid ethyl-ester, 1,3-diethyl-benzene, cyclopentene, heptane, cis-dichloroethene, trans-dichloroethene, cyclopentane, cycloheptane, 1,2-propadiene, carbon oxide sulfide, 2,2,3-tri-methylbutane, tetramethylbenzene, 2,4,5-trimethylphenol, 2-methyl-2-butene, tetramethylbenzene, 2~4~6-trim~thyl-o wos2Jl6~88 PCT/~IS92/0215~ -phenol, pentylbenzene, trimethyl-pentane, decamethyl-cyclo-pentasil-oxane, 1,3-dichlorobenzene, hexadecane, 2-methylthiophene, 3,3-dimethylpentane, 3-methyl-2-butene, 2-methyl-1-burene, 2,2,3-trimethyl-pentane, 2,3-dimethylpentane, 2,3,4-trimethylpentane, 2,6-dimethylphenol, 1,2,3-trimethylbenzene, 2,3-dimethyl-pyridine, 2,3-dimethylhexane, 3-chlorobenzaldehyde,

3-methylhexane, 2,4-dimethylhexane, 3-methylheptane, (Z)-2-butene, 2-methylhexane, trimethylbicyclo-heptane, (E)-2-heptene, 4-methylnonane, tetrachlorobenzene, butene, chloronitrobenzene, dichlorobenzene, dichloroethene, tetramethyl benzene, bromopropane, dichloro-1-propene, chlorobenzenamine, dimethylcy-clohexane, dichloronitrobenzene, dichloronaphthalene, dimethylcyclopentane, bromoethylbenzene, dichloro-methyl-benzene, benzenedicarboxaldehyde, benzoyl nitro peroxide, bromochloropropane, dibromo-chloro-propane, pentachlorobutadiene, dibromochloropropane, 2-butoxy-ethanol, bromopentachloro ethane, tetradecamethyl-cycloheptasiloxane, trimethyl-pentanediol, dodeca-methylcyclo-hexasil-oxane, hexamethylcyclotri-siloxane, octamethylcyclo-tetrasil-oxane, hexadecamethylcyclo-octasil-oxane, tridecane, tetradecane.
A "high solids formulated coating composition" means a nonaqueous formulated coating containing not more than about 400 grams of volatile organic substances per liter of formulated coating composition and preferably less than about 300 grams of VOCs per liter of formulated coating composition. "Film"
is formed by application of the formulated coating to a base or substrate, evaporation of solvent, if present, and cross-linking. "Air-dried formulated coating" means a formulated coating that produces a satisfactory film without heating or baking. "Ba~ed formulated coa~ing~

W092/16588 ~ 6 ~ PCT/US92/02155 means a formulated coating that provides optimum film properties upon heating or baking.
Although many of the polymers and copolymers exhibit LC-like properties, the criteria for liquid crystallinity is varying. The X-ray structure analysis can in certain instances prove liquid crystallinity, but such analysis is costly and the results are sometimes ambiguous. Less costly techniques are widely used to gain evidence for the presence of liquid crystallinity 1o and to study it. The most common are - polarizing microscopy, - differential scanning calorimetry (DSC), - dynamic mechanical-thermal analysis (DMTA), - wide angle X-ray scattering (WAXS), and - rheological studies.
The quality of evidence of liquid crystallinity obtained from such studies may range from quite convincing to highly questionable in a given instance.
Often a singlè technique, such as polarizing microscopy or DSC, can provide very strong, if not absolutely unchallengeable, evidence that a given polymer is liquid crystalline.
Given the above situation, applicants do not necessarily assert the polymers, polyesters and adducts thereof and polymeric vehicle of the invention are liquid crystalline. They may be, but rather, applicants assert that the polymers, polyesters and adducts thereof and polymeric vehicle of the invention exhibit liquid - crystalline-like properties, or alternatively provide a polymeric vehicle with desired hardness and impact resistance. As used herein a composition or polymer exhibits liquid crystalline-like or liquid crystalline properties if at minimum a substantially homogeneous WO9~/16588 PCT/US92/0215~--compound or polymer displays first order transitions at two different temperatures by DSC.

HY~roxyl Terminated Polyester~ Of The General Formula -Nonaqueou~ 8y~tems Broadly in one aspect of the invention, the hydroxyl terminated polyester of Formula I is dispersed in a media such as a mono-oxirane adduct of the polyester of the general Formula I, an organic solvent and cross-linking agent with a dispersant such as a nonionic surfactant or lecithin to provide a formulated coating composition which provides unique coating binders with properties as previously described. The cross-linking agent is required and is in an amount effective for providing the coating binder and the media is in an amount effective for providing the dispersion for a low VoC formulated coating composition. Dispersants may or may not be required to complete or stabilize the dispersions.
In one aspect of the invention using an organic solvent as a part of a low VOC nonaqueous formulated coating composition, the polymeric vehicle of the invention comprises a cross-linking agent together with from about 20 to about 92 weight percent, based upon the weight of the weight of the polymeric vehicle, of an organic solvent dispersible oxirane adduct of a hydroxyl terminated polyester having LC properties and having the general Formula I:
` I. HO-V-Al'-(W-Ar-X-Al-Y)_ -Ar'-Z-OH
m wherein o V= -C- or a covalent bond;
Al' = (CH2) n or a covalent bond;

`~O 92/16~88 ,~ ~ 3 `- j! ~ g P(~r/US92/02155 O O
Il 11 W= -CO-, -OC- or a covalent bond;

Ar = ~ or O O
X = -C0- or -OC-Al = (CH2)n O O
Il 11 Y = - C0- , -OC- or a covalent bond, 1l but if X = -0-C- and if V s bond, and if Al' = bond, and if W = bond and if Z - bond, then Y =
ll --CO--;

Ar' _ ~ or o co~ol-n~ bond; ond ll Z ~ -C- or a covalent bond wherein ~ii= 1 to 20, but when V - bond, Al' = bond, W = bond and Z = bond, ~ > 2 n = 2 to 20.
The above polyester is hydroxyl terminated where O o V ~ - C - , Z ~ - C - and Al' = (CH2)n or bond and Ar' = - ~ or ~ or bond, but if Al' = bond then Il 11 W = -C0- or bond and if Ar = bond then Y = -C0- o*-bond.

The remainder of the polymeric vehicle optionally may comprise other polyesters. Cross-linking agents which may be used in such nonaqueous systems are aminoplasts, amines, regular and blocked di- and polyisocyanates and epoxies.
The hydroxyl terminated polyesters of the above general formula such as (CH2 ) n ( \ ~ C~ o -- (CH2)n ~) m (n = 4--16, m = 2--5) have low or no dispersibility in most common organic solvents, such as xylene or toluene. According to the invention, however, these hydroxyl terminated polyesters may be modified with a mono-oxirane having not more than 25 carbon atoms to provide an oxirane adduct of the polyester, which modified polyester (or adduct) is dispersible in organic solvents. The polyester modified to the oxirane adduct may be used either alone or as a blend with the polyester of the general formula along with a cross-linking agent to provide a polymeric vehicle which is dispersible such as in ~n organic solvent. The blend which includes the polyester, modified polyesters and cross-linking agent are particularly important in providing polymeric vehicles which are a part of a high solids formulated coating composition.
In making the oxirane adduct of hydroxyl terminated polyesters, it is preferable to first carboxylate the hydroxyl terminated polyester and then react it with the oxirane as described in other portions `~ 0 92/16588 ~ ;`) PC~r/US92/02155 of this specification. This is an adduct of the poly-ester of general Formula I according to the invention.
In another important aspect of the invention, hydroxyl terminated or diol polyesters of the general formula can be part of non-aqueous dispersions including high solids coatin~ dispersions by combining the diol polyester with a reactive diluent. Broadly the reactive diluent is a hydrocarbon organic liquid having from about 2 to about 5, preferably 2, functional groups such as carboxyl and hydroxyl, preferably hydroxyl. Through its functional groups, the reactive diluent is capable of reacting with the cross-linking agents described herein (preferably an aminoplast or polyisocyanate) and has a viscosity at about 25 C. of from about 0.5 Pa-s to about lS 25 Pa-s. The reactive diluent includes a reaction product of (1) an aromatic hydroxy acid or diacid such as terephthalic acid, para hydroxy benzoic acid or 2,6-naphthalenic acid with a mono-oxirane having not more than 25 carbon atoms such as the oxiranes described in connection with making a modified polyester by grafting a mono-oxirane thereon, or (2) the reaction product of a straight chain aliphatic diacid having 4 to 14 carbon atoms with the cyclohexyl diol 1,4-dimethylol cyclohexane which has the structure HOH2 ~ CH2OH or the reaction product of 1,6 cyclohexane dicarboxylic acid with a straight chain diol having 4 to 14 carbon atoms. In the case of the aromatic acid, the oxirane and the aromatic acid such as terephthalic acid are reacted in stoichiometric amounts with heating and a catalyst such as triphenyl benzyl phosphonium chloride (TPBPC). While not intending to be bound by any theory, mono-oxiranes having bulkier structures such as O o / \ 11 CH2--CHCH2-OCC~

6 ~
WO92/16~88 PCT/US92/0215~--as will be further described herein provide a diluent which appears to stabilize the dispersion through steric stabilization. In this connection a particularly useful diluent is the reaction product of terephthalic acid and a mono-oxirane sold under the name of Glydexx N-lO from Exxon Chemical Company. The reactive diluent also appears to be capable of association with the polyester and solvent for further stabilization. Moreover, the reactive diluent is difunctional which permits it to participate in the cross-linking rea~tion of the polyester and cross-linking agents such as melamines and polyisocyanates during curing. The dispersions formed with the reactive diluent and diol polyesters of the general formula are stable at solids levels of from about 40 to about 80 weight percent.
Where reactive diluent is used as a part of dispersions according to the invention, polymeric vehicles comprise the hydroxyl terminated polyester of the general formula together with amounts of reactive diluent and cross-linking resins in amounts effective for providing a coating binder having a pencil hardness of at least about 3H and a reverse impact resistance of at least about 60 inch-lbs. at a binder thickness of l mil.
Generally, where reactive diluent is used the polymeric vehlcle will have at least about lO weight percent and preferably at least about 25 weight percent of the reactive diluent. Dispersants such as lecithin, a nonionic surfactant, or adduct of the polyester of Formula I together with organic solvents also may be added to the formulated coating composition to stabilize the system.

~092/16588 PCT/US92/0215 Hvdroxvl Terminated ~olvest~rs Of The GeDeral Formula -Aqueous 8vstQms.
In yet another aspect of the invention where the polyester is hydroxyl terminated or a diol, that polyester may be made dispersible in an a~ueous solvent.
To disperse the hydroxyl terminated polyester in an aqueous system, the hydroxyl terminated polyester of the general formula is carboxylated with a polyacid or anhydride, the anhydride being preferred, with a stoichiometric amount or less of the acid or its anhydride. In a particularly important part of this aspect of the invention, from about lO to about 50 mole percent of the stoichiometric amount (the amount of acid or anhydride that would be required to have one acid or anhydride molecule react with each available hydroxyl on the polyester) of polyacid is particularly effective in providing the carboxylated polyester having an acid value in the range of at least about 30 to provide water dispersibility after the polyester is converted into an amine salt. The polyester may be carboxylated with trimellitic anhydride, phthalic, succinic and maleic anhydrides or polyacids such as adipic and isophthalic acid with trimellitic anhydride being preferred.
In this aspect of the invention, the amine salt of the carboxylated hydroxyl terminated polyester of the general formula will provide a water dispersible polymeric vehicle which comprises a cross-linking resin reactive with the amine salt of the carboxylated polyester. The amine salt comprises from about 20 to about 92 weight percent, based upon the weight of the polymeric vehicle, of the water dispersible amine salt of the carboxylated polyester. The crsss-linking agent in the polymeric vehicle is an a~ou~t effective for cross-linking the carboxylated polyester to provide a coating o~
W O 92/16588 PC~r/US92/02155 -`

binder having a pencil hardness of at least about 3H and a reverse impact resistance of at least about 60 inch-lbs. at a binder thickness of l mil. Generally, the cross-linking agent will comprise at least about lo to about 50 weight percent of the polymeric vehicle. Cross-linking agents which may be used in the aqueous system generally are the same as those used in the aqueous system except that unblocked isocyanates can not be used in the aqueous system and blocked isocyanates can be used only with difficulty in an agueous system.

Carboxyl Terminate~ Polyo~ter~ Of The Goneral Formula -AcrueouQ ~ystemQ.
In another aspect of the invention the carbox~l terminated polyester of the above general formula permits a water dispersible polymeric vehicle. In this aspect of the invention, the polymeric vehicle comprises a cross-linking agent together with about 20 to about 92 weight percent, based upon the weight of the polymeric vehicle, of an aqueous solvent dispersible polyester which is the amine salt adduct of the acid terminated polyester of the above general formula. This amine salt polyester has LC properties and provides a coating binder having a pencil hardness of at least about 3H and a reverse imPact resistance of at least about 60 inch-lbs.
at a binder thickness of 1 mil. In this aspect of the invention, the genexal Formula I defines the acid terminated polyester where V and o Z = - C -; or where V, Arl, Al' and Z all are covalent bond then O O
Il 11 W = - OC - and Y = - C0 -. In this aspect of the ~092/16588 i~ ~g~ PCT/VS92/021 invention, the remainder of the polymeric vehicle may optionally comprise other water dispersible polyesters or amine salts thereof. As previously stated, cross-linking agents which may be used in this aqueous system are generally the same as those used in the nonaqueous system except that unblocked isocyanates can not be used in an aqueous system and even blocked isocyanat~s are used only with difficulty in an aqueous system. The cross-linking agent is used in an amount effective for providing the coating binder with the hardness and impact resistance as previously described.

CarboxYl T~rminated PolYestors Of The Gener~l Formula -Nonaqueous ~yst~ms.
Broadly in one aspect of the invention as to the carboxyl terminated polyester of the general Formula I, these polyesters are dispersed in a media such as a mono-oxirane adduct of the polyester of the general Formula I, an organic solvent and cross-linking agent with a dispersant such as lecithin or a nonionic surfactant to provide a formulated coating composition which will give a coating binder with properties as previously described.
The cross-linking agent may form part of the media and is in an amount effective for providing the coating binder, and the media is in an amount effective for providing the dispersion for a low VOC formulated coating composition.
Dispersants may or may not be required to complete or stabilize the dispersions.
In an important aspect of the invention, to make the acid terminated polyester of the general formula dispersible in many nonaqueous systems, it is reacted with the mono-oxirane having not more than 25 carbon atoms with heating to form a modified polyester which is an oxirane adduct of such polyester. (If the polyester W O 92/16588 PC~r/US92/02155 -`

of the general formula is hydroxyl terminated, the carboxylated form thereof, e.g. is made with a polycarboxylic acid or anhydride such as trimellitic, phthalic, succinic and maleic anhydride with trimellitic anhydride. This carboxylated form is reacted with the oxirane to form ~uch adduct.) In connection with general Formulas II and III, set forth infra, the hydroxyl terminated polyesters may be carboxylated to an acid value in the range of from about 5 to about 230.
Thereafter the carboxylated polyester is reacted with the mono-oxirane. The oxirane adduct of the acid resin as previously de~cribed with nonaqueous systems including the mono-oxirane adduct of the hydroxyl terminated polyesters.

The Mono-O~irane Adduct Aspect Of ~be Invention The invention contemplates dispersions of or which include the mono-oxirane adducts of the polyester of Formula I as formulated coating compositions. The medium for the dispersion may include the mono-oxirane adduct, reactive diluent, cross-linking agent or organic solvents. The mono-oxirane reacted with a carboxyl terminated polyester or the hydroxyl terminated polyester (which is carboxylated prior to reaction with the mono-oxirane) may be propylene oxide, ethylene oxide, butylene oxide, phenylglycidyl ether, butylglycidyl ether, styrene oxide or the glycidyl esters of C-6 to C-22 mono acids.
A particularly useful oxirane in the invention is a glycidyl ester of a C-10 oxo acid represented by the general formula / \ 11 where R represents a mixture of aliphatic groups, the three R groups in the oxirane having a total of 8 carbon ~092/16~88 ~'~'Ji~J PCT/US92/021~5 atoms. That oxirane is commercially available from Exxon Chemical Company under the name of Glydexx N-lO.
The amount of mono-oxirane grafted onto either of the carboxyl or hydroxyl terminated polyester of the general formula will vary from about 0.2 to about 2.0 or more moles of oxirane per mole of polyester, but the amount of mono-oxirane used should be effective for making the polyester of the general formula dispersible such as in non-aqueous organic solvents such as hydro-carbon solvents, aromatic solvents, esters and ketones.In general at 25-C., the modified polyester will comprise at least about lO mole percent and preferably from about 25 to about 50 mole percent of the oxirane radical bonded onto the polyester. High mole-cular weight aliphatic oxiranes are more efficient dispersing agents in ali-phatic solvents. The modified polymer may be designed with the oxirane to disperse in less expensive hydro-, carbon solvents which are more likely to effectdispersion of modified polyesters with long chain oxi-ranes. Long chain oxiranes may adversely affect liquidcrystalline or other properties which will cause the use of a shorter chain oxirane and a shift to a stronger solvent such as an aromatic or ketone. The invention contemplates the use of solvent blends and even the use of more than one oxirane to make the modified polymer.
~ he modified polyester which has mono-oxirane grafted thereon may be a media for a dispersion of the polyesters of general Formula I (as opposed to the adducts ~hereof) together with cross-linking agent. The modified polyester which has the mono-oxirane grafted thereon also may be dispersed in a nonaqueous solvent media by itself or may be mixed into a blend with an unmodified polyester of the general formula where the amount of modified polyester is effective to disp~rse all ~ ~0J ~
WO 92/I6588 PCr/US92/Ot15~ --of the polymeric vehicle of the blend into the solvent.
For a polyester of the general formula which has been reacted with a stoichiometric amount of mono-oxirane, the blend of polyester and modified polyester will include at least about 70 weight percent and preferably at least about 80 weight percent modified polyester in dispersions having at least about 50 weight percent modified and unmodified polyester.
Blendinc The Polyestox~ ~ith_Other ~esins.
As described above, polyesters of the general Formula I or amine or oxirane adducts of these polyesters may be dispersed with other polyesters or other coating resins such as epoxy resins, e.g. the carboxyl terminated polyester with a poly functional epoxy resin which serves as a cross-linking agent. In the blends which include poly functional epoxy resins, the oxirane adduct will comprise from about 5 to about 20 mole percent of the polymeric vehicle. In organic solvent ~ystems, the oxirane adduct of the polyesters may be dispersed with other resins reactive with such adduct to provide a polymeric vehicle with L/C-like properties. In aqueous solvent systems, the amine salt adduct of the polyesters of the general formula may be blended with other water dispersible resins reactive with such amine salt adduct to provide a polymeric vehicle. In these circumstances, to maintain the liquid crystalline characteristics of the polymeric vehicle, if the other resins are not liquid crystalline, a minimum of about 30 weight percent, and preferably about 50 weight percent of the polymeric vehicle, based upon the weight of the polyester of the general formula or such polyester as a part of any adduct thereof, i.e. the weight in the latter instance would not include the weight of the mono-oxirane portion of the polyester. This will provide a polymeric vehicle ~hich '~0g2/16588 '' ~ ? PCT/US92/0~155 will result in a coating binder with a hardness and impact resistance as previously described.
8~ec~fic Import~nt Polvester~ A~ A Part Of T~e In~ention Polyesters having the general Formulas II, III, S IV and V are important aspects of the invention as follows.
The oxirane adducts of Formulas II or III or Formulas II or III as part of the previously described reactive diluent are particularly important aspects of the invention.
II
O O
HO(CH2)n --_ O-- C ~ C O(CH2)n --~ OH

III ( n = 4-16 m = 2--5) O O

HO--~3 O-- C (CH2)n -- C--O- ~ O-- H

n = 2--14 m -- 2--5 The amine acid salt and the oxirane adducts of Formulas IV and V are particularly important aspects of the invention where the polyesters are carboxyl terminated.
Iv O -- O O O

HO C --~3 C--O--(CH2)n --O C ~ e3 C OH

n = 4-15 rn = 1-5 W ~ 1~3 ~ ~
092/1 PCT/US92J02155~-o O o HO-- C (CH2)n ~ O-- C--(Cll~n~c--~H

n - ~-16 m ~ 2-5 ~
`~

M~kina Tho PolYester~ Of The Tnvention Broadly the polyesters of this invention are 1,4-arylene monomers such as terephthalic acid and hydroquinone, or a 2,6-arylene monomers such as 2,6-dihydroxynaphthalene, which are reacted with a linear and unbranched aliphatic diacid or diol whose functionality will be reactive with the functionality of the arylene monomer. The polyesters of the invention may be made by condensation of a diacid with diol by transesterification such as transesterification of hydroquinone diacetate or 2,6-naphthalene diacetate with an aliphatic diacid. The polyesters of the invention generally are made by the transesterification of a dialkyl terephthalate with straight chain, saturated aliphatic diols; the transesterification of hydroquinone diacetate with straight chain, saturated aliphatic diacids, direct esterification with straight chain saturated aliphatic diacids, esterification of terephalyol chloride with straight chain, unbranched saturated diols, transesterification of 2,6-naphthalene diacetate with straight chain saturated unbranched diols and esterification usin~ dicyclohexyl carbodiimide (DCC), diacid and diol as previously described. The alkyl is a lower alkyl having four or less carbons. In the ~atter W 0 92/16588 ~ t ~ g PC~r/US92/02155 reactions, any acid halide may be used in lieu of an acid chloride and propionate or butyrate ~lower alkyls having four or less carbons) may be used in lieu of acetate. In this aspect of the invention, the polyesters may be defined as th~e reaction product of the a polymeric vehicle wherein the polyester is the reaction product of an arylene monomer selected from the group consisting of O O
R02C ~ C02R, XC- ~ -CX, hydroquinone, R'C02 ~ -02CR', 2,6-hydroxynaphthalene, ll XC
R~02 ~ o and mixtures thereof and a 02CR ~
straight chain saturated aliphatic diol or diacid having 6 to 17 carbon atoms which diol or diacid is reactive with the arylene monomer and wherein R = alkyl having 1 to 4 carbon atoms or H, R' - alkyl having 1 to 4 carbon atoms and X z halogen.
The polyesters of the invention should generally regularly alternate between aromatic substituents and the straight chain unbranched substituents which separate or space the arylene grsups. As the spacing between arylene groups increaces to increase overall molecular weight, the lower number of repeating units enhances the liquid crystalline like properties of the polyesters which generally will have a number average molecular ~eight in the range of from about 350 to about 4,000 and preferably from about 400 to about 1800 corresponding to about m = 1 to about 5 when n = 6-10 in Formulas II through V. The ~la~

degree of polymerization or the value of -m is controlled by the relative proportions of monomers in the reaction.
For example a 3:2 mole ratio of monomer approximately yields a polyester where m = 2 for the excess monomer.

conver~$on Of T~e Polyester Of The General Formula To A~
Amine 8alt.
In converting the polyester to the amine salt according to the invention, the polyester with a carboxylic acid functionality, or the hydroxyl terminated polyester which has been carboxylated as previously described, is neutralized with an amine to a pH of about 5.5 to about ll, with about 8 to about 8.5 being preferred, to create an amine neutralized polyester which is dispersible in agueous media. In reacting the polyester with an amine, the polyester may be dispersed with a small to moderate amount of organic solvent which is miscible with water (e.g., propoxypropanol or ethanol) and neutralizing amine then being mixed with the dispersed polyester to form the amine salt of the polyester. Mixing may be by mild mixing or shearing.
Alternatively, an amine, such as a liquid amine may be mixed with the polyester and water to create a dispersion of the amine salt of the polyester. Cross-linking agents used with the amine salts of the polyester in an aqueous media should be stable in water and will commonly be melamines.
The amines which can be used to make the amine salts in the invention include primary, secondary and tertiary alkyl amines and include triethyl amine, NH3, N-ethyl morpholine, methylamine, diethylamine, amino-alcohols, such as ethanolamine, diethanolamine, tri-ethanolamine, N-methylethanolamine, N,N-dimethyl-WO92/16s88 ~1 ~J~ PCT/US92/0215 ethanolamine, 3-aminopropanol and their ethers, such as 3-methoxypropylamine.
Metho~s For Provi~ing anti-Baqainq 8~e~r Thinnina AnC
ThixotroDic ~roperties.
Important aspects of the invention also include a method for providing polymeric vehicles with anti-sagging thixotropic and shear thinning properties and a method of providing polymeric vehicles with these properties.
In one aspect, the invention provides a method for increasing the viscosity of a polymeric vehicle which comprises oligomers and is substantially free of polymers having a number average molecular weight greater than about lO,000. As used herein, "substantially free of polymers" means that the polymeric vehicle prior to curing does not have a number average molecular weight greater than about 2,000 or a weight average molecular weight greater than about 6,000. According to this aspect of the invention, the invention provides a method for increasing the viscosity of a polymeric vehicle when the polymeric vehicle is heated above temperatures most preferably as low as about 25 C. The temperature from which the polymeric vehicle is heated and yet increases in viscosity during such heating preferably may be as low as about 50 C and may be as low as about 75-C.
Generally the viscosity increase will be between the latter temperatures and about lOO-C. The method for increasing the viscosity of a polymeric vehicle comprises dispersing the polyester of general Formula I or amine or oxirane adducts of such polyester with a cross-linking agent and a second oligomer to provide a dispersion at about 25 C. which provides a polymeric vehicle with antisagging properties. This addition modifies the oligomeric polymeric vehicle and provides a modifi~d ~ ~ ~d ^~
W092~16~88 PCT/US92/0215~-polymeric vehicle comprising an amount of the composition of the general Formula I or adducts thereof in amount effective for providing a modified polymeric vehicle which has a viscosity which will increase as it is heated from about 25 C., about 50 C. or about 75 C.
Generally to practice the method of this aspect of the invention and provide novel polymeric vehicles and formulated coating compositions that are part of this invention, the polymeric vehicle will comprise at least about 30 weight percent of the polyester composition of the general Formula I and/or adducts thereof. The novel formulated coating composition will be a dispersion which includes the polyesters of Formula I and/or the amine salts of such polyesters and/or the oxirane adducts of such polyesters. The polymeric vehicle will further comprise a cross-linker resin, and may also include other polymeric components which have a number average molecular weight not greater than about 10,000 (oligomers). In a very important aspect of the invention, the cross-linker resin and/or other oligomeric components of the polymeric vehicle together with the compound of the general formula provide a low VOC
formulated coating composition. Indeed, the formulated coating composition (or polymeric vehicle) may not only be low in VOCs, but may be solventless, to wit:
substantially free of or~anic solvent which is a VOC
and/or water. As a formulated coating composition, the solventless formulated coating composition includes catalysts, pigments and other additives. In this connection substantially free of water and/or organic solvent means not more than about 5 weight percent of water or VoCs separately or combined as measured by ASTM
test D-1644-59.

WO92/16588 ~iU~ b ~ PCT/usg2/02l5~

The cross-linker agent and the oligomeric components (in addition to the compound of the general formula or adducts thereof) are reactive with each other to provide a resulting coating binder having a pencil hardness of at least 3H and a reverse impact resistance of at least 60 inch-lbs. at a binder thickness of about 1 mil. In this aspect of the invention the cross-linking agent includes any di or polyfunctional substance reactive with the polyester of the general Formula I or its adducts. The cross-linking agent has a number average molecular weight not greater than about 10,000 such substances including aminoplasts, amines regular and blocked, di and polyisocya~ates. Oligomeric components which may be used additional to the cross-linking resin, but other than the composition of the general formula include polyesters from cyclohexyldiols such as X-Flex 188 and 128 which are available from King Industries, Norwalk, Connecticut, K-Flex 128 being the lower molecular weight product. All of the additional oligomeric components have a number average molecular weight of less than about 10,000.
The method of the invention includes dispersing the polyesters of Formula I and/or the adducts thereof with the cross-linking agent to provide a low VOC
polymeric vehicle which is a dispersion substantially free of polymers having a number average weight of more than about 10,000. The polymeric vehicle and a formulated coating composition have a viscosity which increases as the temperature of the polymeric vehicle (or formulated coating) is increased from a selected temperature, about Z5 C, about 50 C or about 75 C. This viscosity increase avoids sagging after the polymeric vehicle is applied and heated to cure.

~ 3 3~ 6 ~
WO92/16588 PCT/US92/021~5 In another aspect the invention also provides a method for increasing the shear thinning of a low VOC
polymeric vehicle which.also may be a solventless poly-meric vehicle (substantially free of water and/or organic solvent as previously defined). The method of increasing the shear thinning of a polymeric vehicle comprises dis-persing the polymeric vehicle with the polyester of the general Formula I or adducts thereof. This method pro-vides a high solids, low VOC modi.fied polymeric vehicle comprising the polyesters of the general Formula I or adducts thereof in an amount effective for the increase in shear thinning of the polymeric vehicle. The method of the invention provides a modified polymeric vehicle with a viscosity of not more than about 5 Pa s at a shear rate of at least about 3,000 sec1 at temperatures in the range of from about 25-C. to about lOO-C., preferably not greater.than l.2 Pa-s and most preferably not greater than 0.02 Pa-s. ~ost preferably the shear thinning will be at about 25-C, but preferably at about 50 C or at about 75 C. To achieve the shear thinning as provided by the method, the polymeric vehicle will not require more than about 90 weight percent of the polyesters of general Formula I or adducts thereof (with the remaining amount of polymeric vehicle being about lO weight percent cross-linking agent), but will comprise at least about 40weight percent of ~hese polyesters or adducts to not only provide the shear thinning as aforesaid, but also to pro-vide a coating binder having a pencil hardness of at least 3H and a reverse impact resistance of at least 60 inch-lbs. at a binder thickness of l mil. In this aspect of the invention, cross-linking resins are any di or polyfunctional substance having a number average molecular weight not greater than aboùt lO,000 and which are reactive with the polyesters of general ~092/16~88 ~1~ t~ ~ PCT/~S92/02l5 Formula I or adducts thereof as described above. The oligomeric components which may be in addition to the composition of the general formula include K-Flex 128 and 188.
Combining the methods of shear thinning and increasing viscosity at elevated temperatures provides a truly unique polymeric vehicle, especially in the aspects of the invention which provide a low VOC formulated coating composition or a "solventless" coating composition.
Achieving an increase in viscosity at increasing temperatures without using polymers, especially with polymers with heretofore known mesogens, provides the methods and polymeric vehicles of the invention with an importance and uniqueness heretofore not known in the art pertaining to coating binders for protective paint coatings. Moreover, in view of environmental concerns, this importance is magnified when the invention provides low VoC or "solventless" formulated coating compositions.
The polymeric vehicle according to the invention may be used with formulated coatings which are dried at ambient temperature and baked formulated coatings.

W092tl6588 PCT/US92/0215 The following examples set forth exemplary methods of making cligomers, polymers and coatings according to the inventi~n.
FSA~PLE I

ransestor~f~cat~on of Hvdro~uinone diacetate ~itb ~iaoids for Dreparation of COOH-ter~inated ol~aomers.
O O _ _ CH3C ~ OCCH3+HOOC(CH2)nCOOH ~ H~C(CH2)n -C-O ~ OCC(CH2)n COOH

Compound ~esi~nation _ _ 7c_ _ _ _ 7e_ _ _ _ 7g_ _ _ ~ _ n for diacid 6 8 10 m = 2.
Hydroquinone diacetate and a straight chain -~ saturated aliphatic diacid (where n = 6, 8 or 10) in a mole ratio of 2:3, zinc acetate dihydrate (0.0065 ppm) and antimony oxide (0.025 ppm) were placed in a three-neck flask equipped with stirrer, thermometer, condenser, and Dean-Stark trap and nitrogen gas inlet.
The reactants were heated to 230~ C. in a period of 1 hour and kept at this temperature with stirring for another 2 hours. The sample was t~en dissolved in C~2Cl2, precipitat~d by ethanol, filtered, washed by ethanol and dried in oven at 40-C. for 24 hours. Yield was 70-80%.
NMR and FT-IR for 7g: NMR(CDC13) 1.35, v.s. (-CH2-), l.75,s.bro.(-CH2CH2-COO-), 2.4, m(-CH2-COOH), 2.6, s.
(-CHzOOO-C6H4-), 7.25,s.(benzene). FT-IR, 3000 cm~l~s.bro.(-COOH), 291g and 2851 cm~,s,(-CH2-), 1747 and 1191 cm1 s,(-COO-).

~92/16S~8 PCT~US92/0215 ESANPLE I~
Direct Bster~fication of ~Ydroquinono ~ith Diac~ for PreDarat~on 0~- or c008- TerminatQ~
Oli~omers ~0 or Cn~O~.
Hydroquinone and saturated aliphatic diacid in a mole ratio of 3:2 (for hydroquinone-terminated) or 2:3 (for COOH-terminated), xylene (about 8% by weight, for azeotrope with H2 produced), and p-toluenesulfonic acid (p-TSA) (0.2% by weight) are mixed in a three-neck flask equipped with stirrer, thermometer, condenser, Dean-Stark trap, and nitrogen gas inlet. The mixture is heated to 140-C in a period of 1 hour and kept at this temperature for another 6 hours. The temperature is then raised to 170 C and kept there for 4 hours. The sample is recrystallized from hot toluene, washed with acetone, and vacuum stripped at 80'C for 18 hours. Yields are about 60-85%.

~2~MP~
Ester~fication of 2~6~ ydroxY n~p~t~alene ~ith diacid~ for proDarat~on of COO~-terminated oli~omers.
HO ~ oC(~2)nCOOH--~HC(CH2)n r~

~C(CH2)n COOH
_ _ m Compound desi~nat1on _ _ 8e_ _ _ _ _ _ _ _ 8g_ _ _ _ _ n for diacid 8 10 : ~ = 2.
A mixture of the 2,6-dihydroxynaphthalene, straight chain saturated aliphatic diacid (where n = 8 or 10) in a 2:3 mole ratio, para toluene sulfonic acid ~p-TSA) (0.2~ wt.) and Aromatic 150 (about 10% wt.) were ~u~vv WO92~16S88 PCT/US92/0215~ -heated at 230 C. for 2 hours under N2 gas in three-neck flask equipped with stirrer, Dean-Stark trap, condenser, thermometer and N2 inlet. Distillate was collected in the Dean-Stark trap. The reaction product was cooled down to 70-80C. and dissolved in CH2C12 under heatinq and stirring, the hot solution was poured into ethanol, precipitating the white product. Product was filtered, washed with two portions of ethanol and dried at 40-C.
overnight. Yield was 60-70%. NMR and FT-IR for 8g:
NMR(CDC13) 1.3 s.(-CH2-), 1.75 bro(-CH2CH2-COO-), 2.7 w (CHz-COOH), 2.8w (-CH2COO-C6H4-), 5-7 multiple (naphthalene); FT-IR 3041cm bro.(-COOH); 2926 and 2852 cm1 s.(-CH2-), 1757 and 1215 s.(-COO-), GPC: Mn=1.85xl03, M~=3.45x103 for 8e; Mn-1.64x103, M~-3.94x103 for 8g.

~XAMPL~ III
~sterification of 2,6-dihydroxvna~hthalene ~ith diacid usin~ dio~clohexylcarbodiimide ~DCC).

HO~_ ~ ~}N.~OtH0oc~a~2~n)oH ~ (3NH--C--tlH {~) _ _ tHooc(al2)nco ~Q
OOC~2)n~ CO -OH
~ = 2. _ _ m Compound desi~natlon _ _ 2e_ _ _ _ 2g_ _ _ _lOe_ _ _ _ 1~ _ _ _ n for diacid 8 10 8 10 A solution of 2,6-dihydroxynaphthalene (0.05 mole), aliphatic diacid (where n = 8 and 10) (0.075 mol), dicyclohexyl carbodiimide (DCC) (0.0733 mole), para toluene sulfonic acid (p-TSA) ~0.004 mole) and pyridine (150 mL) were tirred at room temperature. After ~la~6~
W092/l6588 PCT/US92/02155 stirring 24 hrs. a white solid was filtered to remove dicyclohexane urea (DCU). The solution was concentrated on a rotary evaporator, the residue was dissolved in CHCl3 and washed with two portions of 10% HCl aq. followed by water until the water was neutral. The solution was dried over anhydrous MgSO4 and filtered. The residue was separated from CHCl3 with ethanol, followed by filteration. Residue was dried in an oven at 40-C.
overnight. Yield was 50-75%. NMR and FT-IR indicate lo that the products formed by the DCC have similar structure as by other methods. As for lOe and lOg, the mole ratio is 3:2 of hydroxynaphthalene and diacid.

A. Prepar~tion of water roducible di~persion for 7c, 7e, 7g an~ 8e, 8g of ~x~mples I ~nd II.
After the above reactions were completed, the products were cooled to 160-C. under stirring. Butyl cellosolve and dimethylethanolamine ~DMEA) were added to reduce the temperature to 110-130-C. The pH was adjusted to about 8 and the latter temperature range was maintained for 30 min. Water was added to yield a water reducible dispersion, which was used without purification. Non-volatile weight (NVW) is determined after 2 hours of drying at 120-C. (the solid content is about 50~, the solvent contains 80% water).

B. ~n~el pr-p~r~tion The water reducible dispersion of the above samples, HMMM (Resimene 731) and p-TSA in a 70/30/0.3 wt. ratio were cast on steel panels and were baked at 175-C. for 20 min. The film thicknesses were an average of 0.004 in. t4 mil).

C. R~sult~ and ~ us~ion D8C:DSC thermograms for 7c, 7e, 7g and 8e, 8g, lOe, lOg generally shcwed two or more transitions ~n ~ ~ 3 ~ 3 heating and cooling, however, 9e and 9g exhibit sin~le peak on heating. The transition temperature of these samples are listed in Table 1. However, the same polymers synthesized by different methods (such as DCC, direct transesterification) had different transition temperatures in DSC. Differences are possibly due to different molecular weight, as an increase of the oligomer molecular weight increases phase transition temperatures.
WASS:Diagrams exhibit three peaks obtained from sample quenched from 5-C. above Tm. For example, the d-spacing of 16.3A in 8e indicates a layered structure:
the d-spacing at 4.08 and 4.35A in 8e are attributable to lateral distances between rigid molecules in the layers.
These data are listed in Table 2.
Experimental results indicate that these polymers appear to have liquid crystalline properties.
Soft methylene spacers have been found to enhance liquid crystallinity in many cases. Because flexible linking groups can exist in multiple conformations, they tend to enable formation of liquid crystals under suitable circumstances.

D. Physical prop-rti-s.
The coatings of water reducible dispersion made from the above polymers have good mechanical properties, as listed in Table 3.

`~092~16~88 ~ S~ PCT/US92/02155 T~ble 1. Thermal properti-s of oligo~ers for 7c, 7e, 7g, 8e, 8g, and 9c, 9g, lOe, lOg.
_________________________________________________________ No. n ~ e ~ t 1 ~ g C o o 1 i n g T1 ~2 T3 T1 T2 7c 6 202.3 220.4232.8 194.~ 220.4 7e 8 133.5 158.6 148.3 119.2 7g 10 131.8 148.4 137.3 119.9 8e 8 138.4 145.3157.1 153.4 125.9 8g 10 130.7 145.6 138.2 122.6 9e 8 133.8 138.9 124.1 9g 10 113.9 112.7 102.8 lOe 8 115.0 128.0143.5 143.1 104.1 lOg 10 113.9 155.1164.9 158.4 146.4 T~ble 2. The po~k~ of ~AS8 for 7c, 7e, 7g an~ 8e, 8g.
_________________________________________________________ No. ~ ~ - 8 p a c i n g ~ ~A) 7c 6 10.85 4.98 4.14 7e 8 14.14 4.28 4.02 7g 10 17.03 4.40 4.09 8e 8 16.25 4.35 4.08 8g 10 17.24 4.29 4.03 T~ble 3. Tho ~ec~an$cal proportio~ of film~ ma~e from the ~ater reduoiblo ~ispor~ion of 7c, 7e, 7g an~ 8e, 8g.
_________________________________________________________ No. Tu~on ~ardnoss lmpact resi~tance (SEN) t~b-ln) D~r-ct Rev-r~e 7c 22 160 60 7e 28 160 120 7g 27 160 60 8e 27 160 160 8g 18 160 160 W092tl6~88 PCT/US92/0215~-~ XAMPL~ IV
~iol~TereDhthalic Aci~ Polyesters Carboxylyic acid functional polyesters were prepared from terephthalic acid (TPA) and linear aliphatic diols as shown below:
O O ~omatic150(8Z) ~ p-T~
3HO -C ~ C-OHt 2~ - (CH2)n-OH - >
160-180 C,2-3h o O C

HO-( C~ C----(CH2)n-o-)2- C ~ C--OH ~A) + 4H20 ~V~) wherein n = 2, 6 and lO for the diol.
The properties of polyesters ~A1:
Appear~ce: milky white solids.
Differential 8canning Calorimetry ~D8C): Two transitions for n = 6, lO (113.0 and 121.8-C.
for n = 6: 89.7 and 105.3-C. for n s lO):
capillary observation indicates solid-liquid transition at the lower transition temperature.

No transition was observed for n = 2 up to 350C. (decompose).
~ . .
X-ray ~iffractio~: Samples quenched from 5-C.
above T~ show several strong peaks at wide angle region, indicating crystallinity at temperatures above Tm.
Bolubility: Insoluble in ketones, alcohols, esters, etc.; slightly soluble in chloroform.

~V092/16588 `" ~~ 5~ PCT/US92/02155 E~AMPL~ IV~
Modifv tbe Dol~ster A wit~ ~n ~DOXy ~o~n ~5 Glydes2 N-lO avail~blo from the ~xxon ~hemical Com~an~.
O O O O O

C ~ C--~CH2)n~-)2- C ~ C--OH + 2 CH2 _ CH~H2-0--C--CR3 (Gbde~x) 160 o C
2-3h O OH o O O OH O

R3C CO~2 C HCH2----( l ~ C O ( ~2)n~ )2 C ~ C--O--CH2 C Ha~2 OC--CR3 tI~B) where R in Glydexx represents aliphatic groups, the three R groups having a total carbon number of 8; TPBPC is triphenyl benzyl phosphonium chloride.
Properti-s of (IVB):
Appear~nce: All grafted polyesters (n = 2, 6, lO) are milky white to light yellow non-transparent viscous liquids.
S-ray diffra¢tion: Several sharp peaks in the wide angle region, indicating crystallinity of these liquid samples.
D~C: two first order transitions at 23.5 and 60.9-C. for n = lO;
two first order transitions at 40.6 and 90.l-C. for n = 6;
no well-defined transitions were observed for n= 2.

Di~persibility: All form stable high solids (60-80%) dispersions in several solvents at room temperature.

n = ~0: 80% solids dispersion in S methylisobutylketone and butyl acetate: 70%
solids in xylene and 2-heptanone.

n = 6: 60% solids dispersion in methylisobutylketone, 2-heptanone, butyl acetate, and xylene; clears to transparent solution when heated to elevated tempexatures below lOO C.

n = 2: 80% solids dispersion in 2-heptanone and butyl acetate; becomes two phases when diluted to 60% solids (a clear top phase and a concentrated dispersion).
ESAMP~ IVb Cross-linkina Pol~ester IVB ~it~ bexa~is (met~oxy~et~yll melami~o re~in ~MMM).
Foroulation:
~olyester (IVB) l.4 g HMMM CoDmercially available : as Resimene 746 0.6 g Para-toluenesulfuric acid (p-TSA) 0.004 g (0-2%) xylene l.0 g B~king condition: 150-C. for 30 minutes.

~092/l6~88 PCT/US92/021~5 Film properties:
n = 10 n = 6 n = 2 Pencil hardness 4H/5H6H/7H 7H/8H
Tukon hardness ~KHN) 9 18 30 Reverse impact resist-ance (inch-pounds) 80 >160 >160 Direct impact resist-ance (inch-pounds) >160 >160 >160 Appearance glossy, glossy,some no defects pinholing fuzzy-looking Film thickness about 1 mil; same thickness for other films.
1~ X-ray: For n = 6, some weak peaks in the wide angle region, indicating some crystal domains:
for n = 2, several sharp peaks in the wide angle region, indicating high crystallinity.

~XAMP~E ~Vc ~ross-linkina PolYester IV~ with a toluene-~iisocyanate pre~olYmor (Mondur C~-60) Formulation (as for n = 10):
Polyester (IVB) 1.27 g (0.0020 equivalents) Mondur CB-60* 0.89 g (0.0022 equivalents) dibutyltine dilaurate 0.0043 g (0.2% w/w) xylene 1.0 Ba~ing con~ition: 70-C. for 30 minutes.
Film propertieQ:
n = 10 n - 6 n = 2 Pencil hardness HB/H 3H/4H 6H/7H
Tukon hardness (KHN) 10 18 30 Reverse impact resist-ance (inch-pounds) 80 >160 >160 Direct impact resist-ance (inch-pounds) >160 >160 >160 Appearance glossy, glossy, some no defects pinholing fuzzy-looking X-rsy: For n = 6, some weak peaks in the wide angle region, indicating some crystal domains;
for n = 2, several very strong sharp peaks in the wide angle region, indicating high crystallinity.
* Mondur CB-60 is an adduct of toluene diisocyanate and a triol.

~XAMP~ V
Terephth~lic ~cid ~TPA)/diol/Polyesters.
Hydroxy functional polyesters were prepared from TPA and diols by the methods shown below.
Method I.
O O
~ Znket~e(02~) 2CH3- O-C ~ C- O- CH3t3HO-(CH2)n-OH >
1~-230C,3h O O

H-(o-~cH~)n -O- C ~ - C) --(CH2)n OH(~) +~CH30H

lO Method II.
O O
44 DCI~, 022 2 HO - C ~ C--OH ~ 3 H~(CH2)n~H
ro~n~mp,18h O O

H-(O-(CH2)n --O--C ~ C ) _~ --(CH2)n-OH O i ~

wherein n = 6, 7, 8, 9, lO, 12 or 16 where DCC represents dicyclohexylcarbodiimide and DCU represents dicyclohexylurea.

'VO92/16588 PCT/US92/021 Propert~es of PolYesters ~Vc):
DSC: Two or three first order transitions on heating and one or more transitions on cooling, typical of LC polymers.
Cross-polar~ 8~ ng microscope: The samples quenched from 5-C. above Tm shows batonnet or grain-,like textures, indicating possible smectic C or nematic structure.
~-ray: Several peaks in the wide angle region and a medium peak in the small angle region, indicating possible smectic C structure.
8O1ubil~ty: Soluble in chloroform and dichloromethane; insoluble in ketones, alcohols, esters, etc.

Esterific~tion ~sin~ DCC for Proparation of PolYestor~ Of tho Tlrpe nGT, ~0, C~IO. and CnGT
here ~GT ~e~ -0~1 t-xmiuat-d Dolyester~ CnGT
m-ans -COO~ ~orm~nat-d Polv,estor, ~0 ~e~ns -0~
Texmi~at-d Polve~tor mad- ~it~ Uvdxoouiuone and Cn~Q ~ s a -COOH ~oly-st-r ~ade ~ith ~vdroc~u~uo~e .
Terephthalic acid (or saturated aliphatic diacid) (0.02 or 0.03 mol), saturated aliphatic diol (or hydroquinone) (0.02 of 0.03 mol), p-TSA (0.0024 mol), and DCC (0.044) is dissolved in 200 ml of pyridine in a single-neck flask with DCC being added last. A white precipitate begins to appear in about 2-10 min., which is dicyclohexylurea (DCU). After stirring at room temperature or elevated temperature (up to 80-C) for 24 to 6 hours, the reaction solution is filtered to remove DCU, concentrated on a rotary evaporator, and dissolved in CH2C12 to remove the remaining DCU. The CH2C12 solution is washed with 3 portions of 10% HCl and 3 portions of water, dried over MgS04, and concentrated to a high concentration tpolyester not precipitated yet). The polyester is precipitated by adding acetone. The sample is dried over vacuum at 60-C for 8 hours. Yields are about 50-90%.

~i~a~
W092/16588 PCT/US9~/02155 P~ v~
ModifY Polyest-r VC ~it~ ~ucc~nic anhY~ride and t~eD with GlYdeYY N-10.

o o o H--1--(CH2)n --O--C~ 1~2----(CH2)n--OH ~2 I ~o C . 2-~ ~

0 O o ~ ~ o o 1 fi ~
H~-- C_ CH2CH2 ~ C ~ (a~2)n ~ C )2 ~ (CH2)n---- C--CH2CH2--C--OH
o ll 0 1PePC (0 5 g/mol) 2 R3C -- C--0--CH2-- CH-- CH2 150 C, 2-3 h o 0 ~ ~ o o 0 = C-- CH2CH2 ~ C--(O--(CH2)n ~ o l ~ ~ C--)2-- --(CH2)n--~ C--CH2CH2-- C = O
O O
2 CH O C--CR3 R3C -- C-- o--aH2--aH_ at~

~) Propertie~ of t~e Glydesx N-10 grafte~ polyester ln = 10):
~pp-aranc-: ~ilky white to light yellow non-transparent viscous liquid, indicating crystallinity or liquid crystallinity in the liquid sample.
lo D~C For n = 10, two transitions (28.7 and 69.8-C.) are observed, typical of LC polymers.
Polarizing ~icros¢ope of quenched ~mple:
grain- and batonnet-like textures, indicating possible nematic or smectic C structures.
~-ray: Several strong peaks in the wide ~angle region and a medium peak at small angles (6.24, ~092/16588 h i ~ ~ ~ b ~ PCT/US92/02155 14.14 A)~ suggesting possible smectic C or cybotactic nematic ~nematic with short-range smectic-like ordering) structure.
8O1ub~1ity: Form stable dispersion in toluene and MIBK (methyl isobutyl ketone) with 60-80%
solids.
BSa~PLg Vb Cro~s-lin~in~ of non-~rafted ~olvester (VC) ~herein n = 10 ~ith ~MMM.
Formul~tion:
Polyester (VC) 1.4 g HMMM ~Resimene 746) - 0.6 g p-TSA 0.004 g toluene 3.0 g ~soluble only at elevated temp.) Ba~ing con~ition: 150'C. for 30 minutes.
Film properties:
Pencil hardness 6H/7H
Tukon hardness 20 KHN
Reverse impact resistance >160 inch-lbs.
Direct impact resistance ~160 inch-lbs.
Appearance fuzzy-looking ESAMP~ Vc Cro~s-lin~inq of Gly~e~x N-10 ~rafted polyester (VD) ~th ~MM ~Resimene 7~6~.
Formulation:
Polyester (VD) 1.4 g HMMM (Resimene 746) 0.6 g p-TSA 0.004 g toluene 1.0 g Ba~ing cond~t~on: 150-C. for 30 minutes.
Film prop-rties:
Pencil hardness 3H/4H
Tukon hardness 20 KHN
Reverse impact resistance 60 inch-lbs.
Direct impact resistance >160 inch-lbs.
Appearance glossy- no defects~

EXAMP~E VI
Tere~hthalio acid/diol~Pht~alic AnhYdride/GlYdexx N-lO modified oli~omer.
5Polyester (VC) (containing a repeating unit of as the cases before) was grafted or reacted with phthalic anhydride (PA) and then with Glydexx N-lO.

H~ ca2)a --O--C ~ ~o_(CH2),--OH t 2 190 C 1-2 h O O - O ~ / O O

HO--C C--O--(CH2)n --O--C ~ ~ C - --(CH2)n---- C~ C - OH
o ll O IPBPC (0 5 g/mol) 2 R~C _ C_ O_ CH2-- CH _ CH2 160 C. 2-3 h 0 ~ /~\ C ~--~CH2)D--O--C ~ ~ --~CH2)n ~ ~ C C = O

CH2 o CH2 HO--CH--CH2--~-- C--CR3 R3C C--O--CH2--CH--OH
(~E) 'V092/16~88 ~J~ 8 PCT/US92/0215 wherein n = 6, lO and 12.

~he properties of th- GlydosY N-~0 grafted oligoest-r ~with n= lO):
Appear~nce: Milky white to light yellow non-transparent viscous liquid.
~-ray: Several peaks in the wide angle region and a weak peak in small angles (6.06A, 14.6 A).
80lubility: Form stable dispersion in toluene with 60% solids.

læS.aMPT E VI~
Cross-linking oli~omer VI~ with ~MMM ~Re~imene 7~6).
Formulation:
Oligoester (IVE) l.4 g HMMM (Resimene 746) 0.6 g p-TSA 0.004 g toluene 2.0 g B~ing condition: 150-C. for 30 minutes.
Film prop-rties:
Pencil hardness 3H/4H
Tukon hardness 12 KHN
Reverse impact resistance ~80 inch-lbs.
Direct impact resistance ~160 inch-lbs.
Appearance glossy- no defects ESAMP~E VII~
TereDhthalic Aoid~d~ol~Tri~ellitio Anhydride Oli~oesters.
The oligoester (VC) (containing 2 repeating units) was grafted or reacted with trimellitic anhydride (TMA~ and then was grafted or reacted with Glydexx N-lO
as shown below.

WO92/16588 PCT/US92/02155 -~

Cl Iz ) --O--C ~ ~o--(CH2 ) n -- ~ ~ ~ \ ~

200 C 2 h O

HO-- C i ~ (C~2)0 --O--C ~ ~1 --(CHZ)~--O--i i--HO

Oh_ C
O C--OH

I I O TPBPC (a 5 9/mOI) 4R3C _ C_ O_ CH2 _ CH_ CH2 18C C. 2-3 h IIH2 _ ~ R3C -- C--O-- CH2--CH_ OH
o o o \ / o O O l2 o=c~ 1 ~--(c~)n -- ~ 1~ C_~ (c- )O--o-- 1 c=o o= r C ~O

O
¦CH2 11 CH2 R3C -- C-- O-- CH2--CH_ OH
~IF) wherein n = Ç, 10 and 12.
The prop~rtios of th~ Gly~egx N-10 gr~fted oligoestor ~it~ n = lO):
~ppsar~c~: Light yellow transparent semisolid.

~092tl6588 ~ â~ PCr/US92/02155 X-r~y: Several peaks in the wide angle region and a weak peak in the small angle region (6.6-, 14.6A) indicating LC structure of the material.
8O1ubility: Form dispersions in toluene with 60-80~ solids.

EXAMP~E VIIb Cross-link oliaomer VIIF wit~ EMMM (Resimene 7~6).
Formul~tion (n ~ 10):
Oligoester (VIIF) 1.4 g HMMM (Resimene 746) 0.6 g p-TSA 0.004 g toluene 1.0 g Baking condition: lSO-C. for 30 minutes.
Film properties:
Pencil hardness 6H~7H
Tukon hardness 15 KHN
Reverse impact resistance >80 inch-lbs.
Direct impact resistance >160 inch-lbs.
Appearance glossy- no defects EXAMP~E VTIc Cro3s-link oliaoo~ter ~VIIF~ wit~
toluenodiisocy~nate ~re~olvmer.
Formulation (n = 10):
Oligoester (VIIF) 1.02 g (0.0030 equivalents Mondur CB-60 1.33 g (0.0033 equivalents) dibutyltin dilaurate 0.005 g (0.2% w/w) toluene 1.0 g 8~king co~dition: 70-C. for 30 minutes.

`1 6 ~
WO~2/16588 PCT~US92/0215 Fil~ proportie~:
Pencil hardness 6H/7H
Tukon hardness 22 XHN
Reverse impact resistance >160 inch-lbs.
Direct impact resistance >160 inch-lbs.
Appearance glossy, no defects XAMP~E VIII
TereD~thalic acid/diol/epoxy modified polyesters.
Glydexx N-10 was directly grafted onto Oligoester (C) as shown below.
O O O

(~ (~2)n ~ --C ~ C )_--O--(CH2)n--OH ~ 2 CH2 ~ C--CR3 o n~c l9Q C
18~

O OH 0 ~ / 0 OH

R3'`--C--0--CH2 C HCH2 ~ 1~2)n C ~ ~ C) ~ ~ (a~)n--0- CH~ C H a~2--0~ C- ~3 ~) Propert~ o~:
appe~r~nCQ: Light yellow, turbid, viscous liquid (for n = 10, 6), typical of LC polymers.
D8C: For n=10, three transitions: 10.3, 47.0 and 64.0 C.
Cro~s-polari~i~g ~icroscopQ: Grain-like structure.
~olubility: For n = 10, 30~ clear solution in toluene; 70% stable dispersion in toluene.

~092/16588 ,.~ ) PCT/US92/02155 BXAMP~ VIII~
~ol~ester VIIIG cross-linked ~ith ~MXM ~Resimene 7~6).
Formulation:
Polyester (VIIIG)1. 4 g HMMM (Resimene 746) 0.6 g p-TSA 0 004 g toluene 1.0 g B~king condition: 150-C. for 30 minutes.

lo Film properties:

Polyester (VIIIG) n = 6 n = 10 Pencil hardness 6H/7H 6H/7H

Tukon hardness (KHN) 25 20 Reverse impact resistance (inch-pounds) 80 160 Direct impact resistance (inch-pounds) >160 >160 Appearance glossy, glossy, no defects no defects Film thickness about 1 mil; same thickness for other films.

X-ray of Resimene 746 cross-linked film (n =

10): a broad refraction peak in the wide angle 2~ region and a weak but sharp peak in small angles (4.93 , 17.9 A), indicating that the film is generally in an amorphous state but also contains some liquid crystal domains.

PI.~ S~

~Y~roouinone~Di~cid/Polye~Lters.

Carboxylic acid functional polyester from hydroquinone (HQ) and linear aliphatic diacids were prepared as shown below.

~ 3~
WO92/16~88 PCT/US92/0215 O O
Il p-15A tO27.
lene (8%) 2 HO ~OH + 3 HO--C--(CH2) n-- C--OH . >
1~ C, 2 h O O O O

HO -- ( C--(CH2) n-- C--~ O)_--C~ (CH2)n --C--OH

(IXH) wherein n = 10.
Properties oS tb- pol~ester with ~ = 10:
Appear~n¢-: Light brown solid.
D~C: Three first order transitions on heating (100.4, 115.0, and 129.8-C.) and three on cooling (93.4, 105.1, and 124.1-C.), indicating liquid crystal behavior.
~-ray: Two sharp peaks in the wide angle region and one sharp peak in small angles, indicating smectic structure.

E2ANPLE IS~
Polv~r IS~ wa~ araSt-d w~t~ Gl~e~x N-lo a~
sho~n belo~.
O O O o O o HO - ( C--(~H2)n-- ¦--~ ) 2--C--~CH2)n-- C--OH t 2 CH2 _ CH-CH2-0--C--CR3 TP~PC ~ lSQC

O OH O O ~ ~ OH

R3C--C--CH2CHCH2~(C~(CH2)n --C--~ ~ )2--C--(CH2)C--C-OCH2 CHCH20--C--t (Kl) ~092/16588 ;~ PCT/US92/0215 The material with n = lO is a yellow brown ` viscous liquid.

E~ANP~ ISb Polymer ISI wa~ cross-lin~e~ with HNMM
(Resimene 7~6).
Formulation (n = lO):
Polyester (IXI) l.4 g HMMM (Resimene 746) 0.6 g p-TSA 0.004 g toluene 2.0 g B~ing cond~tion: 150-C. for 30 minutes.
Film prop-rtie~:
Pencil hardness 3H/4H
Tukon hardness 13 KHN
Reverse impact resistance 80 inch-lbs.
Direct impact resistance 160 inch-lbs.

E~AMP~S S
Diacid~vdro inone~Eposv Modified Polymers Hydroxy functional polyesters were prepared from hydroquinone (HQ) and linear saturated aliphatic diacids as shown below.
Method I.

~ene~R) 3HO ~OH ~2HO--C--(CH2) n C OH 140C 2h O O

HO ~ O--( C _ (CH2) n-- C-- ~ )2 H

~XJ) 6 ~
W~92/16588 PCT/US92/0215 Method II.
O O

4 ~CC, 022 p-T~A
3 HO ~ OH t 2 HO - C- (CH2)n - C~ OH
\ / pyridine, RT, 18 h O O

( C--(CH2) n--C-- ~ )2--H

(XJ) wherein n = 4, 6 and 10.
Properti-s of the polye~ter with n = 10:
Appear~nce: Light brown solids.
D8C: Three first order transitions on heating (85.0, 104.7, and 120.8-C.) and three on cooling (61.7, 85.6, and 103.8-C.), indicating multi~esomorphous liquid crystal behavior.
Cross-d polarizing mioroscope: Brush- and grain-like (quenched from 80-C.) and schlieren (quenched from lOO-C.) textures, indicating possible smectic C and B structures.
X-ray: Three strong sharp peaks in the wide angle region and two medium sharp peaks in small angels, indicating smectic structures.

~092/16588 ~ PCT/US92/02155 BXA~PLE Sa Polyester S ~a~ arafted ~th Glydexx N-10 a~
shown belo~.
o O O

HO~1 C--(CH2) n~ C--~ )2-H +2 CH2--C~ C--CR3 lP~PC 15~C
2h OH O OH

R3C ~ C--~ C1~2 l HCH2- 0 ~ ~ t C~ (~ 2)n C-- ~ )2 a~2 l H ~ - o~ 3 (I) The material with n = 10 is a yellow brown viscous liquid.

~P~ ~
Polyester S~ ~a~ cross-lin~ed ~it~ RMMM
~ Resimene 746).
Formulat~on ~n = 10):
lo Polyester ~XK) 1.4 g HMMM (Resimene 746) 0.6 g p-TSA 0.004 g toluene 2.0 g B ki~g co~itio~: 150-C. for 30 minutes.
Film properties:
Pencil hardness 3H/4H
Tukon hardness 13 KHN
Reverse impact resistance 80 inch-lbs.
Direct impact resistance 160 inch-lbs.

~ ~ u t~

~XAMPL~ XI
Bvnthesis of IIOOC ~ OC(CH2)10 -- co _~ COOH

A mixture of HOOC-(CH2)10 - COOH, p-hydroxybenzoic acid (PHBA), methansulfonic acid (MSA) and Aromatic 150 (a mixed alkyl benzene solvent commercially available from Exxon Chemical Company) are heated under N2 in a 3-neck flask equipped with stirrer, Dean-Stark trap, condenser and thermometer. The PHBA/diacid mole ratio is 1/2 and 0.1 wt.% of methanesulfonic acid is used. The amount of Aromatic 150 is adjusted to maintain the temperature at 220-230-C.; about 10 wt.% is needed. Distillate (cloudy H2), usually 95-99% of theoretical amount, is collected in the Dean-Stark trap during 5-7 hr. The reaction mass are cooled to 115-C., and methylisobutylketone (MIBK) are added for easy handling.
The reaction mass are directly poured out from flask into a sample can at about 200-C.
The crude product is dried in oven at 120-C.
and cooled and ground. The product is washed 3-4 times with methanol and centrifuged if necessary. Then oven drying and grounding is applied repeatedly. The purified product is dried overnight in oven at llO-C.
The yield varies, but is about 10% or higher.

WO92/16588 ~ PCT/US92/0215 EXAMPL~
8ynthosis of ~olv ~exanediol terephthal~e.

H~ (C~2)6 --E ~3 C-- O (C112)6 m = 2 Two moles acid chloride of terephthalic acid o o (Cl C ~ C - Cl) and three moles of l,6-hexanediol [HO (CH2) 6 OH] are placed in a l00 mL
flask equipped with a distillation extender, a septum, and a stirring magnet. The flask is flushed with argon for 15 min. then heated in an oil bath at about 150-C.
The HCl in the argon flow can be monitored by pH paper -a more quantitative method uses a basic solution ofknown normality and allows the argon flow to bubble through. The solution is then titrated and the extent of reaction can be calculated. The reaction time is about 4 to 8 hours.

~ i Q ~

E2AMP~ 2III
Non-Aoueous Disperslon 0~ Modified Polvester An~
Blend Of Polvester or Ge~eral Formula And Mo~lfied Polye~ter.

SITI~a) - Polyestor ~avina ~C-Li~- P~operties The diol polyester having the formula o O
Il 11 Ho-(cH2~6-(o --C ~ C----(CH2)6 --) OH Q~lll~) ~ 4 H20 m - 2 was made as follows.
59.1 g (0.50 mol) 1,6-hexanediol, 58.3 g (0.30 o o mol) dimethyl terephthalate (CH~O C ~ COCH3). and 0.235 g (0.2% w/w) zinc acetate d~hydrate (ZnAc.2H20) were charged to a 250-mL flask equipped with thermometer, stirrer, nitrogen gas inlet, and Dean-Stark trap. The mixture was heated to 200-220-C. in about one hour and kept at this temperature range with stirring until no more condensed liquid came out (in about 1 to 2 hours).
The material was dissolved in hot acetone, recrystallized, filtered, and dried at 70 C. in an oven for 5 hours. 75 g white solid was collected tyield:
76.0%); NMR indicates the expected molecular structure and a repeating unit of x = 2Ø As a by-product, 15 g lower molecular weight (n c 2.0) polyester was collected after evaporating the filtered acetone.

~SAMP~ SIII~ Mo~ifie~ Pol~ester ~av~ng LC~ e Pro~erties The polyester (XIIIa) was modified with the mono-oxirane Glydexx N-10 by carboxylating the polyester ~092/16~88 ~ PCT/US92/02155 and reacting the carboxylated polyester with the oxirane as follows.
o o Q~
H-(0-(c~)6 o l ~ c)-~ - (CH-2)6 - OH t 2 O\ ~C -180 ~C 2h O

O O O `~ ~ O O O
C--~(al216 --o--C~Cl_--O-lc~ --C~

/ \ ~PC ~05g/n~) ~R3C --C_ o_ C~ CH_ CH2 150- lBO C, 2-3 h l H2 ll R C ~ j--O--C~12--CH--OH

O O ~ ~ O O O
o~ O~ k -O-II~l)-~(02)6-~11~1 0 O~C C~O

¦¦ CH2 HO--CH--CH2--O--C--CR3 ~ l m - 2 W092/16~8~ ~ PCT/US92/02155`

61.5 g (0.1 mol) XIIIa and 38.4 g (0.2 mol) trimellitic anhydride were charged into a 250-mL flask equipped with stirrer, thermometer, water condenser, and nitrogen gas inlet. The mixture was heated to 180-C. in one hour and kept at this temperature for another hour.
100.0 g (0.40 mol) Glydexx N-10 and 0.20 g triphenyl benzyl phosphonium chloride (TPBPC, 0.20 g/mol epoxide) were added. The mixture was heated at 150-180-C. for 90 minutes. The sample was diluted with 150 g toluene, poured into a 800-mL beaker, and washed with 3 portions of 400 mL petroleum ether with the supernatant liquid being recanted each time. The washed sample was then dissolved in 300 mL toluene and the precipitate (if any) was filtered out. The solution was concentrated on a rotavap and then heated to 150 C. to remove all the solvents. The final product (XIIIb) was light-yellow transparent liquid at higher temperatures and non-transparent semi-solid at room temperature. Yield was 162.0 g (81%). The expected structure, as shown above, was verified by NMR spectroscopy.

EXAMPL~ SIII(c~ - Comparative Polye~ter ~ithout LC-Li~e Pro~rties A diol polyester without LC-like properties was made as shown below. That polyester was carboxylated and then modified with the oxirane Glydexx N-10 as shown below to provide the oxirane modified polyester XIIIc.
Synthesis of oxirane modified XIIIc '0 92/16588 , ` PCI/US~2/02155 ItO -- (CH2)6 -- 01~ ~ 2 O~
0~

150 CZ~ 2H20 30 n"nut~
O O

H--(O_PH2)6 --O-- CC ) --O--(C~2)6 -- OH

C ~ C--OH 100 C
0~ 11 O
O o O O O O
Il 11 11 \ / 11 11 11 HO _ C C_ ~O_~CH2)6 --O-- C ~ C )_-- O--(C~12)6 --O-- C C-- OH

OH_ C C-- OH
Il 11 o O
Il \ rP8PC (0.5 9~n~01) ~R3C -- C-- O_ CH2 _ CH-- CH2 150-- 100 C. 2--3 h XIIIc HO--CH--CH2--O-- C-- CR ~
Cr2 O ~R3C -- C-- O-- CH2_ C~_ OH

O~ O-~CI1~ O~ 7)6--lI~ O

O= C (~0 HO --CH--CH2-- -- C-- GR~
R~IC -- C-- O-- CH2_ Ch-- OH
= 2 WO92~16S88 PCT/US92/021 29.62 g (0.20 mol) phthalic anhydride and 35.45 g (0.30 mol) 1,6-hexanediol were charged into a 250 mL
flask equipped with nitrogen gas inlet, thermometer, Dean-Stark trap, and condenser. The mixture was heated to 150-C. in 30 minutes and kept at 150 C. for another 30 minutes. 0.13 g ZnAc.H20 (0.20% w/w of monomers) was added and the temperature was raised to 200-230-C. and kept at this temperature range until no more condensed liquid came out (in about 1 hours: 2.8 g water was collected). 38.4 g (0.2 mol) trimellitic anhydride was added and the mixture was heated at 150-180-C. for 1 hour. 100.0 g (0.40 mol) Glydexx N-10 and 0.20 g TPBPC
(0.20 g/mol epoxide) were added and the mixture was heated at 150-180-C. for an additional hour. The sample was diluted with 150 g toluene and poured into a 800 mL
beaker, and washed with 3 portions of 400 mL petroleum ether with the supernatant liquid being decanted each time. The washed ~ample was dissolved in 300 mL toluene and the precipitate (if any) was filtered out. The solution was concentrated on a rotavap and then heated to 150-C. to remove all the solvents. The final product was light-yellow transparent liquid at room temperature.
Yield was 182.0 g (91%). The expected ~tructure of XIIIc was identified by NMR spectrum.

PROP~RTIE8 OF DI8PER8ION8 OF PO~YM~R8 SIII ~, b ~ c Dispersio~ or 801ut~on Preparation ~A) Formation of Dispersions o~ SIIIa ~n~ SIII b ~O-c. .~ O ~
1.9 g of XIIIb + 0.10 g of XIIIa ~ > melt - -->

W092/16~88 PCT/US92/021~5 -> Homogeneous solution > Stable dispersion ~il~c~11~rb~ (60% solids) 1.9 g of the modified polyester XIIIb and 0.10 g of the polyester XIIIa were charged into a glass vial (uncovered) and heated on a Bunsen burner until the polyester XIIIa completely melted. 1.33 g xylene was added slowly, forming a homogeneous solution. The solution was cooled at room temperature with good shaking (or with ultrasonication), until dispersion formed.

~B) SIIIb Only 1.33 9 xyla~e hent on ~t~n 2.0 g XIIIb > > Homogeneous solution c~li~ ~.~ > Turbid solution (or dispersion) st~y ~t r~ to~. for 1 ~y (60% solids) 2.0 g of the polyester XIIIb and 1.33 g xylene were charged into a glass vial and heated on a steam bath until the polyester XIIIb was completely dissolved. The solution was well shaken while cooling at room temperature. A dispersion was gradually formed during cooling, while some of the polyester XIIIa precipitated on the bottom. However, the solution became a homogeneous turbid solution (or dispersion) after 24 hours.

Instru~eDtal ~ethods ~s~d In Test~ng Described I~
Esample ~III
lH-NMR spectr~ were measured at 34-C. at a Varian Associates EM 390 NMR spectrometer with tetramethyl ~ilicone (TMS) as internal standard.
Viscosity was measured by an ICI cone and plate viscometer. The sample was measured 1 day after preparation. The shear rate was about 10,000 s-l. For WO~2/16588 PCT/US92/021S~ -shear thinning sample, the steady state viscosity was recorded.
Differential scanning calorimetry (DSC) was carried out using a Du Pont 990 thermal analyzer at a heating rate of lO-C./minute and a cooling rate of 2 C./minute. The lower cooling rate and higher heating rate were limited by the instrument. Since a specific cooling system was not available, cooling was accomplished by the atmo~phere. The heating from very low temperature (precooled by dry ice) could not be too slow. The samples were prepared by drying the dispersions at lOO C. for 30 minutes and cooling to room temperature by ~itting in the atmosphere. During DSC
experiments, samples were contained in sealed aluminum pans and an identical empty pan was used as a reference.
Liquid crystal textures and particle distribution of the dispersions were examined at room temperature by an Olympus model BH-2 microscope equipped with crossed polarizers. The liguid samples (as dispersions) were directly examined for particle distribution without evaporation.

Film Ca~ting~Ba~ina And Test~ng Forl~s~mple S~I
The coatings were cast film on lO00 Bonderite polished steel panels with a drawdown bar. The coatings were baked at 150-C. for 20 minutes.
After baking the films were tested l day after cross-linking. Reverse impact resistance, Rnoop hardness ~KHN), acetone resistance, and crosshatch adhesion were measured according to ASTM D2794, Dl474, D2792, and D3359 respectively.

8t~bility Of The Di~er~ions Of ~s~plo SIT~
When hot solutions of mixed polyester XIIIb and polyester XIIIa in xylene were cooled down to room temperature with ~ood shaking, turbid dispersions were W~92/16~88 ~ PCT/VS92/02155 formed; no precipitates other than dispersed particles were observed. Most of the dispersions prepared were stable for at least l day. After several days, some dispersions were still stable, but some separated into two layers (phase separation), the one on the top with lower concentration and the other on the bottom with higher concentration. However, after good shaking or stirring, the phase-separated samples became homogeneous dispersions again. Table 4 in this Example shows the stability of the dispersions after one week of preparation. With the increase in the insoluble polyester XIIIa content, the dispersion became less stable, possibly because less amount of soluble polyester will be available to stabilize the insoluble polyesters, causing poorer stability. Stability also increased with the polymer concentration (or percent solids), possibly because of the higher viscosity of the liquid phase at higher polyester concentration.

Table ~ . 8tability o~ bl-~d o~ SIIIa ~d SIIIb ~ rl ~lene 20 dispersions a~ter 1 l~-elc.

XIIIa in polymer blend 2.5% 5%7.5% 10% 12.5% 15% 20% 30% 40% 50%
-------------__________________ 50% polymer blend-in dispersion SD sD PS PS PS PS PS PS PS PS
_________________________________________________________ 60% polymer blend-in dispersion SD SD SD PS PS PS PS SS SS SS
_________ _______________________________________________ 70% polymer blend-in dispersion SD SD SD SD SD SD SD SS SS SS
_________________________________________________________ where SD = stable dispersion; PS = phase separation; SS =
semi-solids.

o W092~16588 PCT/US92/0215 The mec~anisms for the stabilization of the dispersions are not clear. However, dispersion stabilization is possibly due to the steric effect caused by the bulky alkyl groups on polyester XIIIb. Some polyester XIIIb molecules will co-crystallize with polyester XIIIa during the dispersion formation (as will be discussed later). Many of them will be on the particle surface, with the LC segment associated with the particles and the alkyl groups "dissolved" in the liquid phase, causing entropic (or steric) ~tabilization.
For a comparison study, non-liquid crystalline polyester XIIIc was used to replace XIIIb to prepare dispersion. When a hot solution of polyester XIIIc and polyester XIIIa (XIIIc:XIIIa = 9.1) in xylene was cooled down with shaking, solid species precipitated out. No homogeneous dispersion, as for XIIIb and XIIIa in xylene system, was obtained. The crystallization of the insoluble polyester in a transitional non-aqueous dispersion caused flocculation, possibly because the dispersant (sol~ble polymer) could not co-crystallize with the insoluble polyesters and was excluded from the crystal. Such results suggest that in order to form stable dispersion in the current system, the soluble polyester should have a segment with similar (LC) structure to the insoluble polyester. This common structure provides the sites for association between the soluble and insoluble polyesters, possibly through LC
association.

Vi~005~t~ ~s. Co~tont of Polyastor X~ In ~ho D~porsio~s Viscosity of the dicpersions varies with the co~tent of the polyester XIIIa in dispersions of the blends of polyesters XIIIa and XIIIb. In three different concentrations of the blend (50, 60 and 70%), the increase of XIIIa content cau~ed the viscosity to W092/16~88 ~ ~3~ PCT/US92/0215 decrease to a minimum and then increase again. Since polyester XIIIa is insoluble in xylene, it must stay as dispersion (in solid particles), possibly stabilized by soluble oligomer molecules. Apparently, the viscosity change is accompanied by the formation of dispersions (solid phase) and the decreasing solution concentration (liquid phase). While not intending to be bound by any theory, this can be explained as follows.
For the same percent solids, with the increase of insoluble polyester XIIIa content, the soluble polyester XIIIb is reduced. Thus, the liquid phase concentration is diluted. If the solid phase (dispersion) were not existing, the solution viscosity would decrease. However, the solid phase (dispersion) also contributes to the viscosity, causing higher viscosity than the liquid phase alone. Therefore, the viscosity change is the net result of both the decrease due to the decreasing liquid concentration and the increase due to the increasing solid phase (dispersion).
It is known that the viscosity of polymer solutions usually increases slowly at lower concentration but increases dramatically at higher concentration. This is also true in dispersions of XIIIb. Experiments demonstrate that at high concentration (50-70%), with 10 concentration increase, the viscosity increases 260%.
Thus, at higher concentration, a small reduction in the concentration would reduce the viscosity greatly. On the other hand, for a solid dispersion in liquid at lower concentration (0.30%), the viscosity varies with the solid volume fraction (V) according to the Vand equation ` (an extension of the Einstein equation):
Relative viscosity = 1 + 2.5V + 7.3SV2 +
Viuco ity of dispersion where Relatlve VlSCoslty =
3S Visco~ity of ~iquid ~ iU " `~

According to this equation, for a dispersion at lower concentration (0-30%), the viscosity only increases moderately with the concentration. For example, when the dispersion concentration increases from 0~ to 10%, the viscosity increases 32% (2.5 x 0.1 + 7.35 x 0.1): and when the concentration increases from 10% to 20%, the viscosity increases 47~. Such a viscosity increase is much less than the increase for a polymer solution at higher concentrations (260% increase in viscosity with 10% concentration increase (from 60~ to 70%)). ~hus, for the same percent solids at higher polymer concentration, with the increase in the solid phase (dispersion) to a certain extent, the viscosity should decrease.
The solid phase may be higher than expected when only considering the insoluble polymer, since some soluble polyester XIIIb may co-crystallize with polyester XIIIa and involve in the solid (dispersion) phase. Thus, the viscosity reduction may be different from prediction of the Vand equation.
The viscosity of the dispersions of blends of polyesters XIIIa and XIIIb increased again when the insoluble polyester content (relative to the total polyester) exceeded 10-20%. This is possibly because at higher dispersion concentrations the particles are too crowded to move freely, causing higher viscosity.

Liqu~ CrYsta~linitY of Polyesters ~IIIa ~n~ SIIIb The DSC thermogram of polyester XIIIa showed three first-order transitions on heating and three first-order transitions on cooling, indicating its multimesomorphous property. The lower-temperature mesophase is possibly smectic and the higher-temperature mesophase is possibly nematic. The different intensity ratios among the three peaks on heating from those on cooling can be explained in terms of the different relaxation rates of the transitions on heating from those `V0 92/16588 ,~ a ~ ~ ~ PCI`/VS92/021 on cooling. The three transitions on heating are about the same possibly because all the three relaxation rates on heating are fast enough to be well observed at the experimental heating rate (assume the three transition energies are about the same); while on cooling the two lower transitions are much weaker than the higher-temperature transitions possibly because the relaxation rates of the two lower-temperature transitions are too low to be observed fully at this experimental cooling lo rate. This difference in the transition intensity ratios on heating from on cooling also indicates the good purity of the polyesters, since if each transition were due to different polyesters (varying in structure or molecular weight) there should be no difference between the transition ratios on heating and on cooling.
Polyester XIIIb was non-transparent semi-solid or viscous liquid at room temperature and transparent liquid at elevated temperatures (above 50-60 C.). The non-transparency at room temperature is possibly due to crystal (possibly LC) formation. The DSC thermogram of polyester XIIIb has three first-order transitions (2.6, 43.0 and 59.0-C.) and a second-order transition (-18.3-C.) on heating, while no transitions were observed on cooling above 50-C. (below 50-C., DSC can not be carried out on cooling in this instrument). The two transitions at 43.0 and 59.0-C. are possible due to the phase transitions of the LC units, since the LC unit is the only part in the XIIIb molecule with such high transition temperatures (the melting/freezing point for pure Glydexx N-lO is less than -20-C.) and these two transition temperatures are close to the transition temperatures of polyester XIIIa. Also, these transition temperatures are in the same range for polyester XIIIb to become transparent. Thus these transitions must be crystal or LC transitions. The somewhat lower transition temperatures of the LC units in polyester XIIIb are due W092/16588 PCT/US92/0215~-to the modification by soft spacers (Glydexx N-lO). The clearly separated two transitions due to polyester XIIIa units in polyester XIIIb indicates its LC behavior, the upper temperature being clearing point and the lower temperature being melting point. The second-order transition (-18.3 c.) is typical of glass transition.
The first-order transition at 2.6-C. is possibly the melting point due to the non-LC part of the material.
This temperature is higher than the melting/freezing temperature of pure Glydexx N-lO (-20-C.) due to the attachment of this molecule onto the high Tm units which makes the Glydexx N-lO unit less mobile, causing higher transition temperature.

Morphology of Polye~ter SI~Ic: a Non-~C Oligomer ~ith 8tructur~ 8imilar to Poly~ster ~I~Ib Polyester XIIIc was synthesized as a non-LC
oligomer for comparison studies of the LC properties of polyester XIIlb. Polyester XIIIc is transparent semi-solid or viscous liquid at room temperature instead of turbid semi-solid or viscous liquid as for polyester XIIlb, which may be due to non-crystallinity of XIIIc above room temperature. The DSC thermogram of polyester XIIIc does not have first-order double or triple transitions from -60 to 150-C., indicating non-liquid crystallinity of this polymer. The sharp first-order single transition at 8.2 C. is typical of a melting point, while the weak and broad transition at -17.6'C. is possibly a glass transition. Thus, the two carboxylic acids being in the para positions (as for terephthalate) is important for the formation of LC-like properties:
similar polymers with carboxylic acids in the meta positions will not be liquid crystalline.

W092/16588 ~1 ~J~l 6 ~ PCT/US92/021~5 ~o-Crystalli~ation of Polyestor XIISb ~th Pol~ester SIIIa In order to clarify the possible co-crystallization of polyester XIIIb with Polyester XIIIa in the dispersions, a DSC is carried out for the dry mixed sample (no solvent) containing polyester XIIIa and polyester XIIIb with different polyester XIIIa content. A dry sample is used in the DSC experiment because of the instrumental limitation. However, from the dry samples, we can know the co-crystallizability of polyester XIIIa with polyester XIIIb and thus predict the possible co-crystallization in the dispersions.
DSC thermograms of mix-melted samples of polyesters XIIla and XIIIb were taken with different lS polyester XIIIa content. The DSC plot for pure polyester XIIIa and polyester XIIIb were also compared with DSC
thermograms of the blends. Both the transitions due to polyester XIIIa (higher temperature region) and polyester XIIIb (lower temperature region) are seen in the thermograms for the mixed samples, indicating the existence of two types of LC domains. However, the transition temperatures for the domain for polyester XIIIb is higher than for the pure polyester XIIIa and increase with the increasing polyester XIIIa content;
while the transition temperatures for the domain for polyester XIIIa is lower than for the pure polyester XIIIb and decrease with decreasing polyester XIIIa content. Also the transition temperatures are generally broader than for the pure oligomers. This indicates the involvement of the other polyester in either LC domain.
That is, a polyester XIIIa LC domain also contains some polyester XIIIb molecules, while a domain for polyester XIIIb also contains some XIIIa polyester molecules. For the dispersions, the involvement of the XIIIb polyester in a XIIIa polyester LC domain will lead to the stabilization of the dispersion, since the XIIIb ~ 3~

polyester also contains soft alkyl groups which will cause steric stabilization of the dispersions.

Crosse~ Polari~ing ~ioroscopo 8tudios of Dispersions of the XIIIa and SIIIb PolyQster Bl-nds Microscope studies have been carried out for blends of XIIIa and XIIIb polyesters in xylene dispersions with different XIIIa polyester content (l0, 20 and 30 weight percent). The dispersions were 50 weight percent polyesters. Original wet samples were directly used for the studies. Without crossed polarizing lenses, the samples were found to be transparent. Thus polarizing lenses were used for all the samples, and only the birefrigerant parts of the samples showed up in the microscope observation.
Polyester XIIIb in xylene showed a few scattered birefrigerant particles in the solution or dispersion;
while with the addition of polyester XIIIa, more birefrigerant particles were presented which indicates the induced LC formation by the XIIIa polyester. The particle size was very small at lower XIIIa polyester content; while larger particle size was observed when the XIIIa polyester content is high. With higher XIIIa polyester content, the particles are stabilized by less amount of polyester XIIIb and have more chance to coalesce with each other; while at lower polyester XIIIa content the particles are stabilized by more polyester XIIIb and remain as smaller particles. This also explains the better stability of the dispersions with lower polyester XIIIa content. For the dispersions with l0 and 15~ polyester XIIIa contents, Brownian motion indicates these dispersions are deflocculated. This Brownian motion may also cause stability of the dispersions.

W092/16588 ~ ) PCT/US92/0215;

Propertios o~ EMMM-Cross-l~nked Films ~ada From Polyestsrs XIIIa ~Dd SIIIb Table 5 in this Example shows the film properties of the polyesters cross-linked with hexakis (methoxymethyl) melamine resin (HMMM). No significant differences in film properties were observed with different polyester XIIIa contents. This indicates that polyester XIIIb gives as good properties as polyester XIIIa does. Although there are some soft groups on polyester XIIIb, it has 4 functional groups instead of 2 as for polyester XIIIa. More functional groups will give higher and more efficient cross-linking, and thus compensate the softness caused by the alkyl groups on polyester XIIIb.

6 ~
WO 92~16588 PCr/USg2/02155 `-O ~ C ~ C
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O .
P ~ 3 W ~ ~ ~ 3 ~ I 3 :~
H I ~1 1 O
H O ~ ~0 1 0 0 0 0 0 . o X O ,c~ I ,.~ O O O o H ~ l ~`
_ I ~ O
~J ~!o ~ E~ 1 O ~ O ~ D ~ ~

~ i ~ ~/ ~ G
h-rl I ~ ~ Ui S
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E~
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b ~1 O O ~1 1 ~ ,, ~ ~ C C

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I O J~
~ ~ I ~ 3 O 1:1 ~ I C:
u. ~ ~ a ~ _ o ~ ~ gd I ~ O
m ~ I C~
#
~ _, ~092/16588 ~ PCT/US92/021S~

All the films are transparent and very glossy.
Because these LC oligomers have lower melting and clearing points than the curing temperature, they were cured from isotropic state. The cross-linked films may remain isotropic or have smaller LC domains (smaller than light wavelength). Such a film appearance is very desirable in coatings.
All the films showed good hardness and excellent flexibility. However, the Tukon hardness of these films was not as high as for other LC coatings, possibly because the LC domains did not form after cross-linking.
Stable non-aqueous dispersions can be formed from blends of a polyester of the general formula and a modified polyester. LC association between the soluble and insoluble polymers and the steric effect of the soluble polymer may be the causes of the dispersion stabilization.
At the same polyester blend concentration, the insoluble LC polyester induced dispersions showed lower viscosity than the pure soluble polyester solution. The viscosity showed a minimum when the insoluble polyester content is 10-20% of the total polyester content. This rheological behavior can be explained in terms of Vand equation together with the fact that the viscosity of polyester solutions at high concentrations increases significantly with the concentration increase. This viscosity reduction is important for making higher solids coatings.
HMMM-cured films of the dispersions of the polyester/modified polyester blend showed good mechanical properties and excellent appearance (transparent~. This shows that the dispersion formation does not affect the film appearance.

W092/16588 PCT/US92/021~5 PL~ S~V
~ Reactive Diluent ~_p~ol pol~estor) IV(~) - 8y~t~sls of Roactl~ D~lu-nt A reactive diluent having the formula OH OH

R3C- C - - CH2 CHCH2- O- C ~ C- - ~ ~CH2- - C- CR3 wherein R = aliphatic group with ~ having a total of eight carbon atoms, was made as follows as a reaction product of terephthalic acid (TPA) and the mono-oxirane, Glydexx N-10.
O O

HO-- C~ 1--OH CH2--CH-CH2-0--~--CR3 (TPA) (G~dexx N-10) (ca,o~) 10-20 minutes OH \ / OH O XIVa R3C--C--O--CH2 CH CH2 o C ~ ~ C---- CH2 CH CH2--O--C--CR3 1033.2 g TPA (0.20 mol), lOO g Glydexx N-lO (0.40 mol), and 0.2 g triphenyl benzyl phosphonium chloride (TPBPC) (0.5 g/mol) were charged into a 250-mL flask : equipped with thermometer, stirrer, and water condenser.
The mixture was heated with stirring to about 220-C. in about one hour and kept at this temperature for lO to 20 minutes (the TPA solid phase disappeared quickly after the temperature reached 220-C., indicating complete rea~tion). The material was p9ured out into a 300-mL

W092/16588 ~1 U~ 6 ~ PCT/US92/02155 beaker, and washed with several portions of petroleum ether which was added carefully with stirring. The supernatant liquid was decanted after each washing. The washed samples were then heated to lOO C. with stirring on a heating plate in a hood to remove all the solvent.
The final product XIVa was light yellow viscous liquid.
ICI viscosity: 2.4 Pa s. at 50-C., and >lO Pa s. at 25-C.
Yield was 92.5%.
The diol polyester having the formula XIIIa was made by a procedure similar to that described in XIIIa for preparation of the non-aqueous dispersion. A second diol ester having the formula -- O O --HO-- (CH2)1o O--C ~ C--O (CH2)1o m m = 2 also was prepared for further preparation of a non-aqueous dispersions.

Pre~ration of Non-Aqueous Dis~ersions ~sina Rea¢tiv- D~luont XIV~
DisDorsion of Polvester S~Sa ia ~aotiv- Diluent X~a l.0 g polyester XIIIa I l.Og reactive diluent XIVa >
~140-C 21.5 9 to~w.e - > melt > Homogeneous solution ~ > Stable dispersion ~ilec~li~
l.0 g of polyester XIIIa and l.0 g reactive diluent XIVa were charged into a glass vial (uncovered) and heated on a Bunsen burner until the polyester ~IIIa ~UJ~

completely melted. 1.5 g toluene was added slowly, forming a homogeneous solution. The solution cooled down at room temperature with shaking (or with ultrasonica-tion). Dispersion was gradually formed during cooling.
This dispersion was very stable at room temperature and exhibited shear thinning and thixotropic behavior.

D~spers~on of Polyester SIVb ~ ~eact~v D$1uent ~IVa 1.0 g polyester XIVb + 1.0 g reactive diluent agent ~ 140-C 2.0 9 xyla~e 1 0 9 I~IYW
XIVa --- > melt > > >
0.006 9 p-TSA
Homogeneous solution > Stable dispersion.
~l~ter cool~ng 1.0 g of polyester XIVb and 1.0 g of reactive diluent XIVa were charged into a glass vial (uncovered) and heated on a Bunsen burner until the polyester completely melted. 2.0 g xylene was added ~lowly, forming a homogeneous solution. 1.0 g HMMM was then dissolved in the solution. The solution was well shaken while cooling down at room temperature. Dispersion was gradually formed during cooling. This dispersion was very stable at room temperature and exhibited shear thinning and thixotropic behavior.

~lear Coatings Formulated coatings were prepared with similar procedure as described above. The formulated coatings were cast as films on a 1,000 ~onderite steel panel and baked in an oven at 150-C. for 30 ~inutes.
Fo~oul~tio~ 1: Polyester XIIIa 1.0 g Reactive diluent XIVa 1.0 g H~ 1.0 g Toluene 1.5 g p-TSA 0.006 g ~092/16588 ~i G' ~ PCT/US~2/0215 Film properties: Tukon hardness 10.0 KHN
Pencil hardness 3Hf4H
Reverse impact 160 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil Appearance glossy, no defect Formulat~on 2: Polyester XIIIa 1.0 g Reactive diluent XIVa 1.5 g HMMM 1.5 g Toluene 1.5 g p-TSA 0.006 g Filu propert~es: TuXon hardness 10.0 XHN
Pencil hardness 3H/4H
Reverse impact 120 in-lbs.
Direct impact 160 in-lbs.
Fil~ thickness 1.0 mil Appearance glossy, no defect Formulation 3: Polyester XIIIa 1.5 g Reactive diluent XIVa 1.0 g HMMM 1.0 g Toluene 2.5 g p - TSA 0. 006 g Fil~ propert~-~: Tukon hardnes~ 12.0 KHN
Pencil hardness 4H/5H
Reverse impact 160 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil Appearance qlossy, but poor leveling WO92/16588 PCT/US92/0215~-Formulation ~ ~cro~s-lin~Qd by polyi~ocyanate):
Polyester XIIIa 1.0 g Reactive diluent XI~a 1.5 g Mondur CB-60 2.5 g Toluene 1.5 g 150-C./ 90-C./
30 ~in. 2~hrs.
Film properties: Tukon hardness 18.0 XHN 18.0 KHN
Pencil hardness 4H/5H 4H/5H
Reverse impact 160 in-lbs. 160 in-lbs.
Direct impact 160 in-lbs. 160 in-lbs.
Film thickness 1.0 mil 1.0 mil Appearance glossy, fuzzy-no defects looking 15 P~omented Coat~ngs Polyester XIIIa and the reactive diluent XIVa were charged into a 300-mL aluminum can. The polyester was melted by heating on a Bunsen burner with care. Half of the calculated amount of toluene was added, followed by the HMMM and an AB dispersant, Elvacite AB-1040.
While cooling down at room temperature, the ingredients were shook until the transparent material became a milky dispersion. A TiO2 white pigment from du Pont, Tipure R-960, and p-TSA were added. The formulated coating was dispersed on a high speed dispersing mill for 30 minutes.
The second half of the toluene was added during the dispersing. The formulated coating composition exhibited thixotropic behavior.
The for~ulated coating compositions were cast as a film on a 1,000 Bonderate steel panel and baked at 150-C. for 30 minutes (Formulation 1) or 10 minutes (Formulakion 3, with more catalyst added).

WO92/16588 f~ S~ PCT/US92/02155 Formulation 1: Polyester XIIIa 30.0 g Reactive diluent XIIa 30.0 g H~MM 30.0 g Tipure R-960 48.0 g Toluene 90.0 g p-TSA 0 30 g Elvacite AB-1040 3.60 g Byk-020 (defoamer from Mallinckrodt) 1 drop 10 Film properties: Tukon hardness 10.0 KHN
Pencil hardness 6H/7H
- Reverse impact 40 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil lS Appearance no evident defects, medium gloss Formulation 2: Polyester XIIIa 10.0 g Reactive diluent XIIa 20.0 g HMMM 15.0 g Tipure R-960 22.5 g Toluene 45.0 g p-TSA 0.225 g Elvacite AB-1040 3.38 g Film properties: Tukon hardness 10.0 XHN
Pencil hardness 3H/4H
Reverse impact 80 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil Appearance fairly glossy W092/16588 PCT/US92~02155`

~XPLB S~
NonaquQou~ Di~per~io~ Coatings ~s~ng A ~ouble Rinq_Cycloaliphat~c_2 lILC a~ ~ Reacti~e Diluent.
The LC-like polyester XIIIa of Example XIII
having the structure:
O O

H- (O-(CH2)6 - O- C ~ C)_ - O -(CH2)6 - OH m =2 and a non-LC composition (R-Flex 188 commercially available from King Industry) having the structure:
O

HO-CH2 ~ ~H20 C (~2)n -C-O-C~ ~CH2-OH n = 5-7 were made into nonaqueous conversion coating compositions and studied as described below.

Preparation of Nonaq~eous ~ispers on Example 1 1.0 g XIIIa + 1.0 g K-Flex 188 > melt ~ w~ ~
> Homogenous solution > Stable dispersion 1.0 g XIIIa and 1.0 g X-Flex 188 were charged into a glass vial (uncovered) and heated on a Bunsen burner until XIIIa completely ~elted. 1.5 g toluene was ~0 added slowly, forming a homogenous solution. The solution was cooled at room temperature with good shaking (or with ultrasonication). Dispersion was gradually formed during cooling. After several weeks of storage, the dispersion separated into a dilute top phase and a concentrated bottom phase (no solid precipitates were ~O9/16S88 ~1 U~L~ 8 PCT/US92/021 observed); the solution returned to homogeneous dispersion after minor shaking or stirring. This dispersion was very stable at room temperature and no change was observed 3 months after preparation. The dispersion exhibited thixotropic behavior.

~xamplo 2 l.0 g XIIIa + l.0 g K-Flex 188 140 C.> melt 2.0 9 xy~e~
1 0 9 Resim~e 746 ~ h~king > Homo. solution - > Stable dispersion O . 00~ 9 p-TSA on co~l irq l.0 g XIIIa and l.0 g R-Flex 188 were charged into a glass vial (uncovered) and heated on a Bunsen burner until the oligoester completely melted. 2.0 g xylene was added slowly, forming a homogenous solution.
l.0 g Resimene 746 was then dissolved in the solution.
The solution was well shaken while cooling down at room temperature. Dispersion was gradually formed during cooling. This dispersion was very stable at room temperature and exhibited thixotropic behavior. No change was observed after 3 months except that the dispersion separated into a dilute top phase and a concentrated bottom phase; the phase separation disappeared after minor shaking or stirring.

Cloar Co~tinqs A formulated coating composition was prepared with similar procedure as described above. It was cast film on a l,000 Bonderate steel panel and baked in an over at 150-C for 20 minutes (25-C for l day and 70 C for 2 h fvr Example 4).

~ i u WO92/16~88 PCT/US92/0215 Ex~mplo 3 For~ulation: Polyester XIIIa 1.0 g R-Flex 188 1.0 g Resimene 746 1.0 g Xylene 1.5 g p-TSA 0.006 g Film propert~-s: Tukon hardness 14.0 KHN
Pencil hardness 4H/5H
Reverse impact 160 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil Appearance glossy, no defect Fx~mple ~
For~ulat~on: Polyester XIIIa 1.0 g K-Flex 188 1.5 g Resimene 746 1.5 g Xylene 1.5 g p-TSA 0.006 g Film propsrties: Tukon hardness 12.0 KHN
20 Pencil hardness 3H/4H
Reverse impact 160 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil Appearance glossy, no defect ~amplo 5 For~ul~tion: Polyester XIIIa 1.5 g K-Flex 188 1.0 g Resimene 746 1.0 g Xylene 2.5 g p-TSA 0.006 g `VO92/16i88 ~ PCT/US92/02155 Film properties: Tukon hardness 15.0 KHN
Pencil hardness 4H/5H
Reverse impact 120 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil Appearance glossy, but poor leveling Example 6 ~cros~-lin~ed by an isocyanate prepolym~L
Formul~tion: Polyester XI~Ia 1.0 g K-Flex 188 1.5 g Mondur CB-60 2.5 g Dibutyltin dilaurate 0.008 g Toluene 1.5 g 25 C./1 day 70 C./2 hrs.
15 Film properties: Tukon hardness 16.0 XHN 20.0 KHN
Pencil hardness 3H/4H 4H/5H
- Reverse impact 160 in-lbs. 160 in-lbs.
Direct impact 160 in-lbs. 160 in-lbs.
Film thickness 1.0 mil 1.0 mil Appearance ~lossy, fuzzy-no defect looking Pi~mented Coatincs Cro~s-linked by ~NMM
Polyester XIIIa and K-Flex 188 were charged into a 300 mL aluminum can and were melted by heating on a Bunsen burner with care. Half of the calculated amount of xylene was added, followed by Resimene 746 and ~lvacite A~-1040. While cooling down in the atmosphere, the solution was kept shaking until the transparent material became a milky dispersion. Tipure R-960 and p-TSA were added. The coating composition was dispersed on a high speed dispersing mill for 30 minutes. The W092/16~88 PCT/VS92/0215~--second half of the xylene was added during the dispersing. The formulated coating composition was very stable; no phase separation was observed after 3 months.
The formulated coating composition exhibited thixotropic behavior.
The formulated coating compositions were cast film on a 1,000 Bonderate steel panel and baked at 150C
for 20 minutes.
~x~ple 7 10 Formulation: Polyester XIIIa 10.5 g K-Flex 188 10.0 g HMMM (Resimene 746) 10.0 g Tio2 White Pigment (Tipure R-960) 15.0 g Xylene 30.0 g p-TSA 0.15 g Dispersant (Elvacite A3-1040) 2.00 g Defoamer ~Byk-020) 1 drop Film properties: Tukon hardness 14.0 KHN
Pencil hardness 7H
Reverse impact 80 in-lbs.
Direct impact 160 in-lbs.
Film thickness 0.7 mil Appearance med. gloss, some pinholing ~xample 8 For~ul~t~on: Polyester XIIIa 10.0 g K-Flex 188 20.0 g Resimene 746 15.0 g Tipure R-960 22.5 g Toluene 40.0 g p-TSA 0.23 g Elvacite AB-1040 3.38 g Byk-020 2 drops ~VO 92/16S88 ~ 1 U J ~ ) P~r/US92/02155 Film properties: Tukon hardness 12.0 KHN
Pencil hardness 7H
Reverse impact 80 in-lbs.
Direct impact 160 in-lbs.
Film thickness 1.0 mil Appearance glossy Piomented Coatinos Cross-lin~ed by an Isooyanate PreDol~mer.
Polyester XIIIa and K-Flex 188 were charged into a 300 mL aluminum can and were melted by heating on a Bunsen burner with care. Half of the calculated amount of toluene was added, followed by Mondur CB-60 and Elvacite AB-1040. While cooling down at room temperature, the solution was kept shaking until the transparent material became a milky dispersion. Tipure R-960, Byk-020, and dibutyltin dilaurate were added. The paint was dispersed on a high speed dispersing mill for 30 minutes. The second half of the toluene was added during the dispersing. The formulated coating composition was very stable; no phase separation was observed. The formulated coating composition exhibited thixotropic behavior.
The formulated coating compositions were cast film on a 1,000 Bonderate steel panel and baked at 70'C
for 2 h.
Example 9 Formulation: Polyester XIIIa 10.0 g K-Flex 188 20.0 g Mondur CB-60 30.0 g Tipure R-960 22.5 g Toluene 30.0 g p-TSA 0.23 g Dibutyltin dilaurate 0.18 g Elvacite AB 1040 3.00 g Byk-020 2 drops ~ i ~3 W092/16~88 PCT/US92/0~15 Film properti-~: Tukon hardness 22.0 KHN
Pencil hardnass 7H
Reverse impact 80 in-lbs.
Direct impact 160 in-lbs.
Film thickness l.O mil Appearance fairly glossy ESAMP~ ~VI
Properties as to viscosity, yield stress and sagging were studied as to the following compounds -A LC-like Composition (a) having the formula O O

H-(O-(CH2)6 - o- C ~ C)- (CH2)6 - OH ~=2 which was previously described in connection with polyester VC of Example V;
A LC-like Composition (b) having the formula O O

H-(O-(CH2)10 _ O- C ~ C)_ - O -(CH2)l0 -OH m=2 which was previously described in conn~ction with polyester VC of Example V:

o Vo92/16~88 ~iU~ 3 PCT/US92/02155 _99_ A LC-like Composition (c) having the formula HO--CH--CH2--O-- C~ CR3 IIH2 R3C -- C-- O-- CH2--CH_ OH
O o o o o O
o.c c -(-(CH2)~ -o-c ~ C)_--(CH2~6 -- c l-o o= c c -o :.................. I l HO--CH_ CH2--O-- C-- CR3 II I
R3C -- C-- O-- CH2--CH_ OH
m . 2 and which was previously described in connection with polyester VIIF;
A nonliquid crystalline Composition ~d) having S the formula HO--CH--CH --O-- C-- CR

O O o O
O-C 1--(O-(CH2)~ --o--1~ O- (CH2)6 --O-- 1~ O

o.c c o lo ~CH O

HO --Ctl--CH2-- o-- c-- CR;~ ll l which was generally described in connection with polyester XIII C;

~ J~
W092/16~88 PCT/US92/0215 A LC-like Composition (e) having the formula O O ~ O

~2~H2 C -~O(CH2)6 -O-C ~ C)__O_(CH2)6 -O- C-~CH2- C=O
O

CH2- Cll - CH2----C--CR3 m = 2 R3C--i--~ C~2--CH--CH2 which composition was generally described in Example V.
A nonliquid crystalline Composition (f) having the general formula OH O O OH O
A ~
R3C- C - O- CH2 CHCH2 - o- C ~ C - CH2 CH~2- - C- CR3 which was generally described in Example XIV; and A nonliquid crystalline Composition (g) K-Flex 188 (non-LC; commercial product from King Industry) which has the general formula O O
HO-CH2 {~} CH2 9 C (CH2)n -C- O - GH2 ~CH2-OH n - ~7 and A nonliquid crystalline Composition (h) which has the general formula o O

HO (CH2)6 ~ [ C {~_ CO ~CH2)6 ] -- OH m = 2 ~092/16~88 ~ PCT/US92/02155 TemDer~turo ~opon~ence of t~e Visoos~tY of t~e ~C~ e Oligomers The viscosity of the LC polymers was determined with an ICI viscometer at several temperatures from 25 to 150-C. For thixotropic samples, the steady viscosity was recorded. Tables 6-9 show the viscosity vs. temperature for several LC polymers.
T~ble 6. Viscosity v~. Tempor~ture for Composition ~1 _________________________________________________________ Temperature ( C) 25 50 75 100 125 150 _________________________________________________________ Viscosity (poise) (heating) 1.25 1.00 0.45 0.85 0.45 _________________________________________________________ Viscosity (poise) (cooling) 0.70 0.20 1.40 0.82 0.45 _________________________________________________________ Table 7. ViscositY vs. Tomp-r~ture ~or Compos$t$on tb) _________________________________________________________ Temperature (-C) 50 75 100 (115)* 125 150 _________________________________________________________ Viscosity (poise) (heating) >100 1.5 0.4 46.0 2.5 1.2 _________________________________________________________ Viscosity (poise) (cooling) ~100 1.5 0.6 12.0 2.5 1.1 ____~____________________________________________________ * Estimated temperature.

~L~ J'~O~
WO92/16588 PCT~US92/0215~-Table 8. Visco~ity vs. T~m~erature for ComDosition ~c) _________________________________________________________ Temperature (-C) 25 50' 75 100 125 150 _________________________________________________________ Viscosity (poise) (heating) ~100 34.0 >100 29.5 7.5 1.5 _________________________________________________________ Viscosity (poise) (cooling) >100 89.5 >100 36.5 9.o 1.5 _ _ ______________________ Table 9. Visco8ity VS. Te~perature for Co~position ~e) _________________________________________________________ Temperature (C) 25 50 (65)* 75 100 125 _________________________________________________________ Viscosity (poise) (heating) >100 12.0 15.5 2.0 0.2 _________________________________ _______________________ Viscosity (poise) (cooling) 45 2.0 57.0 16.2 2.5 0.1 __ ____________________ * Estimated temperature.

It is seen from Tables 6-7 of this Example that for the LC-like polyesters the viscosity first decreases and then increases with increasing temperature until a maximum.
While not intending to be bound by any theory, the unusual rheological behavior has been explained as follows. In the LC state, the polymers are oriented and may exhibit much lower viscosity than nonoriented polymers. With increase of temperature, the polymers become isotropic and the viscosity increases dramatic-ally. On the other hand, there is a general tendency for the viscosity of polymers to decrease upon increasing temperature due to ther,mal motion. The results of these competing effects lead to a maximum viscosity upon 092/16588 ~ : o PCT/US92/0215 g~j increasing temperaturP. Alternate explanations, however, are possible.
The LC-like polymers of the invention were compared with the non-LC counterparts. The viscosity of several non-LC polymers with similar structures to the LC-like polymers of the invention was measured. Tables 10 and 11 of this Example show the temperature dependence of Composition (d) and Composition (h) (non-LC
counterparts of Composition (c) and Composition (a) respectively). It is seen that the viscosity decreases steadily with increasing temperature, in contrast to the unusual viscosity behavior of the LC-like polymers.

T~ble 10. Viscosity vs. Temper~ture for Com~os~tion l~) ~non-~C) ________________ Temperature (-C) 25 50 75 100 125 150 _________________________________________________________ Viscosity (poise) (heating) >100 ~100 >100 29.0 7.5 1.5 _________________ Viscosity (poise) (cooling) >100 >100 >100 28.0 5.4 1.8 _________________________________________________________ ~blo 11. vi~c08~ty ~S- ~mporaturo_~Qr Compositio~ on-~C~
_________________________________________________________ Te~perature (-C) 25 50 75 100 125 150 Viscosity (poise) 30 (heating) >100 Z4.5 2.2 0.5 0.1 0.1 ___________________________________________ _____________ Viscosi~y (poise) (cooling) >100 28.5 2.4 0.5 0.1 0.1 _________________________________________________________ ~1~3 Thixotropic Be~avio~ of LC-Li~e Polymers Table 12 of this Example shows the time dependence of the ICI viscosity of Composition (c) at different temperatures. The viscosity in the LC-like region (around 50-C) decreases with time to a steady value, indicating thixotropic properties of the LC-like polymers. The viscosity decrease is possibly due to break-up of certain structure (possibly LC association) with time.
T~ble 12. Visoo~ity vs. ~hear Time of Composition (c) at Different ~empsrature.
_________________________________________________________ Temperature (-C) Visc. (poise)/Shearin~ Time (second) --------------_________________________ 25 >100/0 >100/30 _________________________________________________________ 50 >100/0 30/26 20/60 20/120 _________________________________________________________ 75 >100/0 100/30 .________________________________________________________ _________________________________________________________ -- -------_______________________________ _________________________________________________________ Yiel~ 8tross of LC-Li~e Polymers The yield stress was determined by measuring the relative flow distance of the polymers at different temperatures. 0.2 g of sample was placed on an aluminum panel sitting at 45' angle and the flow distance of the oligomers after 10 minutes was recorded.

Table 13. Flow Distance of ~omposition ~c) At Differont TemDeratures ______________________________ Temperature (-C) 25 50 60 90 150 _________________________________________________________ Flow distance (cm)/10 min. 0.0 o.o 6.4 6.0 9.5 ______ __________________________________________________ WO92~16~88 ~ 3 PCT/US92/0215~

Table 12 of this Example shows the flow distance of Composition (c) after 10 minutes at different temperatures. Although the polymer is viscous liquid or semi-solid at room temperature, no flow was observed up to 50-C, indicating yield stress of the polymer below about 50-C. At 60-C and above, Composition (c) flowed, indicating zero yield stress. Since the transition temperature of Composition (c) is 43.0 (Tm) and 59.0-C
(Tc) (Fig. 4), the flow distance data suggest that the yield stress is possibly due to LC association.

8aggin~ Re~i~tanoe of Coating~ Formulated from LC~ e Polymers.
TeQtina Met~od~
The method of ASTM 4400 was used except that an aluminum panel instead of a chart was used because of higher baking temperature. The sample was cast on an aluminum panel using Leneta anti-sag meter (The Leneta Company), and the panel was set 90- to the horizontal direction at the testing temperature for a designated time (such as 20 minutes). The thickness of the thickest unsagged strip was recorded as the anti-sagging value.

Saaq~ng ~es~stanco of Solv-nt Coating~
at ~levated Tom~erature Example 1 (LC) 25 Formulation: Composition (c) 2.5 g HMMM (Resimene 746) 0.5 g Para toluene Sulfonic acid (p-TSA) 0.006 g Xylene 2.0 g p-TSA 0.006 g iJ O
WO92/16~88 PCT/USg2/0215 Baking conditions: 150-C for 20 minutes.
Sagging Resistance: 6 mil.
Appearance of coating: glossy.

~x~mple 2 (Non-~C count~rpart of ~x~5 Formulation: Composition (d) 2.5 g Resimene 746 0,5 g p-TSA 0.006 g Xylene 2.0 g Baking condition: 150-C for 20 minutes.
Sagging Resistance: 3 mil.
Appearance of coating: glossy.

~xample 3 ~LC) Formulation: Composition (e) 2.0 g Resimene 746 1.0 g p-TSA 0.006 g Xylene 2.0 g Baking condition: 150-C for 20 minutes.
Sagging Resistance: 10 mil.
Appearance of coating: glossy.

Example 4 (LC) Formulation: Composition (c) 1.5 g Polyisocyanate based upon toluene diiso-cyanate blocked with ~-Caprolactam (Desmodur BL-1185A from Hobay Corporation) 1.9 g Dibutyltin dilaurate 0.007 g Toluene 1.0 g Curing condition: 70'C for 1 h.

W092/~6588 ~ 0~ PCT/US92/021 Sagging Resistance: 12 mil.
Appearance of coating: glossy.

8a~ging ResistancQ of 8O1~ent Coatina~
at Room TemDorature

5 EX~mD10 5 tI,C1 Formulation: Composition (c) 2.5 g Mondur CB-60 1.6 g Dibutyltin dilaurate 0.008 g Toluene 2.0 g Curing condition: room temperature for 1 day.
Sagging Resistance: 10 mil.
Appearance of coating: glossy.

Exam~lo 6 (~on-~C) ¢ountorpart of B~mple 4 Formul~tion: Composition (c) 2.5 g Mondur CB-60 1.6 g Dibutyltin dilaurate 0.008 g Toluene 2.0 g Curing condition: room temperature for 1 day.
Sagging Resistance: < 3 mil.
Appearance of coating: glossy.

~aggin~ R~sistanoe of LC-~$ko Nonaqueous Dis~er~ion Coat~ngs at ~l-~at-d T~mperature Example 7 t~C) Formul~tion: Composition (a) 1.0 g Composition (f) 1.0 g Resimene 746 1.0 g p-TSA 0.006 g Xylene 1.5 g WO92~16~88 PCT/US92/02155 Baking condition: 150-C for 20 minutes.
Sagging Resistance: 12 mil.
Appearance of coating: glossy.

Fxample 8 (Non-~C) S Formul~tion: Composition (f) 2.0 g Resimene 746 1.0 g p-TSA 0.006 g Xylene 2.0 g Baking condition: 150'C for 20 minutes.
Sagging Resistance: < 3 mil.
Appearance of coating: glossy.

~UCL
Formulation: Composition (a) 1.0 g Composition (g) (K-Flex 188) 1.0 g Resimene 746 1.0 g p-TSA 0.006 g Xylene 1.5 g Baking condition: 150-C for 20 minutes.
Sagging Resistance: 12 mil.
Appearance of coating: glossy.

Ex~mpla 9 ~Non-~C oounterpart of Ex~mple 9) Formulation: Composition (g) (K-Flex 188) 2.0 g Resimene 746 1.0 g p-TSA 0.006 g Xylene 2.0 g Baking condition: 150C for 20 minutes.
Sagging Resistance: < 3 mil.
Appearance of coating: glossy.

WO92~16588 ~ &~ PCT~US92/02155 8aqgin~ Re~i~tano~ of Nonaqueous ~C-Li~e Disper~ion Coat$ngs Cur-~ at aoom Temperature ExamDle 11 ~C) Formulation: Composition (a) 1.0 g Composition ~f) 1.5 g Dibutyltin dilaurate 0.008 g Mondur CB-60 2.5 g Toluene 1.5 g Curing condition: room temperature for l day.
lo Sagging Resistance: 12 mil.
Appearance of coating: fairly glossy.

ExamDle 12 (Non-~C oounterpart of Fxumple 18) Formulation: Composition (f) 2.5 g Mondur CB-60 2.5 g Dibutyltin dilaurate 0.008 g Toluene 2.0 g Curing condition: room temperature for l day.
Sagging Resistance: < 3 mil.
Appearance of coating: glossy.

EximDle 13 (LC) Formulation: Composition (a) 1.3 g Composition (g) (K-Flex 188) 1.2 g Dibutyltin dilaurate 0.008 g Mondur CB-60 2.5 g Toluene 1.5 g Curing condition: room temperature for l day.
Sagging Resistance: lO mil.
Appearance of coating: fairly glossy.

W092/16~88 PCT/VS92/0215~ -Ex~mple 14 Non-~C counterp~rt of ExamDle 20) Formul~tion: Composition (g) (K-Flex 188) 2.Sg Mondur CB-60 2.5 g Dibutyltin dilaurate 0.008 g Toluene 2.0 g Curing condition: room temperature for 1 day.
Sagging Resistance: < 3 mil.
Appearance of coating: glossy.

Improved 8a5 Resist~nce of Composition l c) ~Soluble LC~ e)_Co~t~ngs ~ith a~itiOn of Composition la) _LL~ yple ~C) Example 15 ~Soluble ~C, t~- 84~e ~S ~a~p~ L
Formulation: Composition (c) 2.5 g lS Resimene 746 0.5 g p-TSA 0.006 g Xylene 2.0 g Baking condition: 150-C for 20 minutes.
Sagging Resistance: 6 mil.
Appearance of coating: glossy.

~xample 16 lAddition of Composi~ion (~ to Compo~ition lc)) Formulation: Composition (c) 1.8 g Composition (a) 0.2 g Resimene 746 1.0 g p-TSA 0.006 g Xylene 2.0 g Baking condition: 150 C for 20 minutes.
Sagging Resistance: 8 mil.
Appearance of coating: glossy.

W O 92/16588 ~ 1 U ~ o PC~r/US92/021 Example 17 ~Addition of Co~position ~a) i~to Composition ~c)) For~ul~t~on: Composition (c) 1.2 ~
Composition (a) 0.8 g Resimene 746 1.0 g p-TSA 0.006 g Xylene 2.0 g Baking condition: 150-C for 20 minutes.
Sagging Resistance: 12 mil.
Appearance of coating: glossy.

Baggi~ Resistan¢- of P~ ntod Coatings ~t ~levatod Tempor~turo ~2~mplQ 1~ (IC) Formulation: Composition (c) 30.0 g Resimene 746 15.0 g Tio2 White Pigment (Tipure R-960 from du Pont) 22.5 g p-TSA 0.23 g Xylene 40.0 g Dispersant (Elvacite AB-1040) 3.4 g Defoamer (Byk-020) 2 drops Baking condition: 150-C for 20 minutes.
Sagging Resistance: 10 mil.
Appearance of coating: glossy.

~s~mple 19 (LC) ~or~ul~tion: Composition (c) 20.0 g Resimene 746 10.0 g Tipure R-960 26.7 g p-TSA 0.17 g Toluene 40.0 g Elvacite AB-1040 2.0 g WO92/16588 PCT/~lS92/02tS5 Byk-020 1 drop Baking condition: 150-C for 20 minutes.
Sagging Resistance: 12 mil.
Appearance of coating: fairly glossy.

5 Ex~mple 20 ~LC~
Formulation: Composition (a) 30.0 g Composition (f) 40.00 g Resimene 746 30.00 g Tipure R-960 48.0 g p-TSA 0.03 Xylene go.o g Elvacite AB-1040 3.6 g Byk-020 1 drop Baking condition: 150-C for 20 minutes.
Sagging Resistance: 12 mil.
Appearance of coating: fairly glossy.

EX~ID1-- 21 lLC) Formulatton: Composition (a) 10.03 g Composition (g) (K-Flex 188) 20.0 g Resimene 746 10.00 g Tipure R-960 15.00 g p-TSA 0.15 a Xylene 30.0 g Elvacite AB-1040 2.0 g Baking condition: 150- C for 30 minutes.
Sagging Resistance: 12 mil.
Appearance of coating: fairly glossy.

6~88 ~ PCT/VS92/0215~
.

Sagginq Re~i~tanoe of Piqmented Coati~gs at ~ower or Room Temperature Exaople 22 ~C) For~ulation: Composition (c) 16.0 g Mondur CB-60 14.0 g Dibutyltin dilaurate 0.05 g Tipure R-960 20.0 g Toluene 20.0 g Elvacite AB-1040 1.4 g.
Byk-020 1 drop Curing condition: room temperature for 1 day.
Sagging Resistance: 12 mil.
Appearance of coating: glossy.

~x~mple 23 (LC) 15 Formulation: Composition (e) 26.3 g Mondur CB-60 22.6 g Dibutyltin dilaurate 0.18 g Tipure R-960 39.2 g Toluene 60.0 g Elvacite AB-1040 3.0 g.
Byk-020 1 drop Curing condition: room temperature for 1 day.
Sagging Resistance: 12 mil.
Appearance of coating: glossy.

- 25 ~x~m~le 2~ t~C) Formul~tion: Composition (a) 5.0 g Composition (f) 10.0 g Mondur CB-60 15.0 g Dibutyltin dilaurate 0.05 g Tipure R-960 20.0 g Toluene 20.0 g Elvacite AB-1040 1.4 g.
Byk-020 1 drop w~A6~8~'~ PCT/~592/021SS

Curing condition: 70 C for 12 h.
Sagging Resistance: 12 mil.
Appearance of coating: glossy.

Although the invention has been described Wit}
regard to its preferred embodiments, it should be understood that various changes and modifications as would be obvious to one having the ordinary skill in this art may be made without departing from the scope of the invention which is set forth in the claims appended hereto.
~s~mple SV~~
8yntbesis of water reducibl- oliqoester derived from dimethyltereDhthalate w$th de~anediol: coating formulation.
~tep 1.
Weight used, g Mole ratio Decanediol 130.0 1.5 Dimethylterephthalate97.0 1.5 Zinc acetate 0.456 0.2% total weight 2.
Oligoester (from step 1) 65.0 Trimellitic anhydride (TMA) 3.46 0.3 Butyl Cellosolve 13.7 --Dimethylethanolamine 6.0 --Water 67.06 --~ teD 1: Into a 0.5-L three-neck flask equipped with stirrer, condenser, Dean-Stark trap, thermometer and N2 gas inlet tube were placed the materials of Step 1. The reaction mixture was stirred and heated under N2 to 150-C.
and then kept at this temperature for 1 hour. C~30H was removed by distillation. After 1 hour the temperature W092/16588 ~ PCT/VS92/0215 was increased to 230 C.; 90% of theoretical amount of CH30H was collected in the Dean-Stark strap during 5 hours. The reaction material was cooled to about so c.
and toluene was added. The hot solution was poured into the bea~er and cooled to 25 C.; the precipitate which separated was collected, dissolved in CH2Cl2, reprecipitated by addition of CH30H, and washed with CH30H. The solid was collected and dried in oven at 120-C. overnight; yield was about 78%.

8tep 2. The solid from Step 1 was placed in to 250-mL
three-neck flask equipped with stirrer, condenser, thermometer and N2 gas inlet tube. The oligoester was heated to about 175-C. and N2 gas flow, and TMA was added.
The reaction mixture had an acid number of about 50 mg lS KOH/g. The resulting oligomer was stirred at 170-180-C.
for about 30 minutes and cooled to 130-C.
Dimethylethanolamine (2 eq. per mole of trimellitic anhydride) was added at 130-C. and then butyl cellosolve was added. The mixture was stirred at 90-lOO-C. for O.S
hour, and water was added to produce an aqueous dispersion which was used without purification; NVW was determined after 2 hours drying at 120-C.

Coatina formulation: The enamel binder was formulated at an oligoester/HMMM/P-TSA weight ratio of 70/30/0.3 and was pigmented at a pigment/binder ratio o.7 with a Tio2 pigment. Dow Corning paint additive 57# and BYK 020 were used at 0.1% of total paint weight to prevent foaming, and help leveling and DuPont Elvacite AB~ dispersant (2 of pigment weight) was used to help stabilize the TiO2.
The solvent used in the paint formulation was butyl cellosolve and water. Pigment dispersion was performed on a high speed disk disperser. But the final grind corresponded to a Hegman value of about 4. The paint exhibited a thixotropic nature.

~V~
WO92/16~88 PCT/US92/021 Coatinas Droperties: The coating was drawn down with a wire-wound bar on steel panels and was baked for 20 minutes at 175-C. The baked coatings had discernable ridges and valleys. Poor leveling was attributed to the thixotropic rheology of the liquid coating. The cured coating had the following film properties.
Reverse impact resistance, in-lb 160 Hardness, Knoop 28 Solvent resistance, acetone double rubs 200 ~AMPL~ SVIII
Rheolo~ic~l Behavior Stu~y on LC-Li~e Oli~omers.
The six compositions studied were:
1. "K-Flex" 188, a commercial reactive diluent sold by King Industries. It is an isotropic liquid. (See Table I) 2. "Resimene 747" a monomeric HMMM type melamine resin sold by Monsanto. It is also isotropic. (See Table II) 3. A blend of lOGT (decanediol terephthalate Com-position (b), ~ = 2), as described in Examples XVI
and V, with K188 (50/50 w/w). This is a blend of LC-like lOGT with isotropic K188. (See Table III) 4. A blend of lOGT, K188, and R-747 (1/1/1 w/w/w).
This blend is a complete 100% solids coatings binder that would cure if baked high enough. The catalyst normally used was left out to prevent reaction in the rheometer. (See Table IV) 5. A blend of 6GT (hexanediol terephthalate, Composition (a), ~ = 2), as described in Examples XVI and V, K188, and R-747 (1/1/1 w/w/w). (See Table V) 6. A blend of 6 GT with X188 (50/50 w/w). (See Table VI) WO92/16588 ~ 6 ~ PCT/US92/021 In~trument: HAAKE Viscometers-Rotovisco RV 100 (HAAKE
Mess-Technik GmbH u. Co., Germany) was used in this study. The temperature was at the range of 25-C. to 125-C. The shear rate was at the range of 252 S-l to 25200 s-l. HAAKE viscometer could not measure high viscosity at very high shear rate. This is a limitation of HAAKE viscometer. The viscosities measured by HAAKE
viscometer were tabulated below.

W092t~ ~ ) PCT/US92/02155 TABL~ I.
~i~cos~ties of ~188 ~t ~ v~r~-ty of tQmper~tures.
~ (P~
Sh- r R-t _ __ ---(~-1) T~ .8C. T U.9-C. T ~ C. T 56.7'C. T8 2S.8 C.
25200 0.05 O.OB 0.21 22680 __0.04 0.08 022 ~ ., 20160 0.04 0.0~ 022 .
_ __ 11 17640 0.04 0.08 022 ~ _ 1S120 0.05 0.08 022 12600 0.06 0.08 0.23 0.41 11340 0.07 0.08 021 . 0.42 _ 10080 0.07 0.08 0.24 0.42 6300 0.07 0.08 0.43 ~ _ 51)40 0.08 o.ag 022 0.71 2520 0.10 0.08 0.57 1.02 2268 0.11 0.60 1.42 , 2016 023 0.57 1.44 . __ 1613 _ 0.17 0.25 1411 0.57 0.23 -.~
2 0 * The ~scosity is too high to be measurable by HAAEOE viscometer.

WO92/16588 ~ i UJ~ ~g PCT/US92/021~

TaBLE II.
The viscos~t~es of Res~eno 7~7 ~t ~ v~r~ety of te~p-r~tures.

Sh--r Rd- . ~ - . - 'I
(~ ') T- 1102C. T ~a~'c T ~ T ~ 2S 7~

2S2C0 0.03 0.05 0.18 .
__ ._ _ 22680 0.03 0.05 0.18 .. _ ..
20160 0.03 0.05 0.18 _ .
17640 0.02 0.06 O.1g 1 0 15120 0.02 0.05 0.18 12600 0.03 0.05 0.20 11340 0.04 0.05 0.21 10080 0.04 0.21 8820 0.04 O.OS 021 . _ 1 5 ~560 0.04 0.05 0.22 6300 0'04 __ 0.22 5040 0.050.23 1.07 _ 4536 0.050.22 1.06 4032 0.040.21 1.04 2 0 3J80 O.OS
3528 _ 021 0.99 3402 0.05 3024 0.05 0.04 020 __ 0.99 2646 0.05 _ 1890 0.04 * 1 he viscosity is too ~igh to bc mcasurablc by HAA~ viscometcr.

TABLB III.
The viscosities of lOGT blen~ed ~ith Rl88 (r~tio l:l by ~-ight).
.
v~ ~-) I
. .. . _ !l ( 1) T~ 114.8qC. T=10Q7~C. T-94.4~. T.9crC. T~UL4 C. T~83.3 C. ~¦
25200 O.OS 0.10 0.12 ~ 0.17 22680 Q06 0.10 0.12 0.26 Q17 21420 _ Q26 _ 1 0 20160 0.06 o~1o------ 0.12 O~B 0.1 17640 _06 0.10 0.13 0.29 0.18 15120 0.06 0.10 0.13 0.30 0.19 12600 Q07 0.11 0.1S 0.32 0.31 11340 0.07 0.11 0.16 0.33 D.32 1 510080 0.07 __ 0.12 0.16 _ 0.3S 0.33 8820 0.08 0.12 Q1~ _ 0.36 _ 0.34 7S60 0.0~ 0.13 0.18 0~3~ 0~36 0.73 6300 O.o7 0.14 0.19 0.41 0.37 0.85 S040 _ 0.08 0.16 ___ 0.23 QS2 _ 0.59 1.01 2 0 536 0.07 0.16 0.2~ O.S6 0.61 1.08 4~32 0.06 0.17 025 0.60 0.64 1.~4 3528 0.06 0.17 02s 0.63 0.68 1.23 3024 0.06 0.18 0.27_ 0.68 0.73 1.31 2016 0.11 0.27 0.37 0.91 124 1.64 2 51814 nO9 0.28 _ Q39 0.95 1.30 __ 1.6S
1613 0.09 0.30 Q3a Q96 1.33 1.64 1~11 0.09 0.32 0.39 1~oe 1.38 1~63 12~9 0.09 0.35 __ 0.38 0.76 1.~2 1.6 ~ The~tyist~ ~ghtobemeas~ablebyHAARE~meter.

W092/l6;88 ~ PCT/US92/0215;

From Table III above, the high-shear viscosities at 88C.
were lower than those at 90-C. The temperature of 88 degrees was the transition temperature from one phase to another phase. This phenomenon is LC-like behavior. The material is shear thinning at temperatures of 102.7-C.
and below, but is virtually Newtonian at 114.8-C.

WO 92/16588 PCr/US92/02155 TAB~ ~V.
The visco~itiE~ of lOGT blon~ed lrith ~188 and Re~imene 747 (r~t~o 1:1:1 by ~reight)O
U~ r Vb~oD nY rP~
RJn~ _ ~- ) T= T= T= T. T~ T~ T~
120.~C.9Q!1qC.86.0q~.~O.O~C.7~.0~C. ~aL~C. SS.S~C.
~00 0.08 22680 0.0 20160 0.08 1 01~640 0.080.29 16380 0.31 _ __ 15120 0.09_0 29 0.35 t4742 0.31 _ ' 13104 0.30 1 512600 0.08 0.40 11466 0.30 11340 0.08 0.39 10080 0.08 0.39 0.55 9828 0.29 2 08820 0.08 0.38 0.54 8190 0.28 7560 O.OB 0.36 0.52 0.67 . .
6300 0.08 0.35 0.49 o.oe 0.090.34 0.41 0.59 0.71 1.08 2 54536 0.090.34 0.40 0.57 0.70 1.06 4032 0.10__ 0.33 0.40 0.5~7 0.68 1.03 3528 0.100.32 0.37 O.S4 0.6S 0.~8 3024 0.110.32 0.36 0.49 0.61 O.gt .
2520 _ 0.48 0.73 _ 3 02268 0.46 _ 0.71 .

2D16 0.11o.74 0.46 0.58 0.65 1.1~ 1.s7 l .. I
1814 0.110.73 0.s7 1.39 _ 1.96 1764 0.59 0.62 1613 0.120.75 0.53 1.35 1.92 3 5 1-11 0.120.77 = 0.51 1.30 1.87 12~9 0.130.76 0.47 1~3 1.~6 * The viscos~ty is too high lo be measurable by HAA~ viscometer.

WO92/16588 . ~ PCT/US92/0215 A dispersion of lOGT in K188 and R747 contains all the elements of a solventless coating binder. As shown in Table IV, such a dispersion exhibits shear thinning at temperatures (86-92 C.) near the phase transition tem-peratures of lOGT. At higher temperatures (120-C.) shear thinning is less pronounced, and at lower temperatures (74-80-C.) the dispersions appear to have approximately Newtonian rheology. Further, at low shear rates (less than about 2100 sec~) the dispersion exhibits a trough in its viscosity-temperature curve, the viscosity increasing from 0.47 Pa-s to 0.76 Pa-s when the dispersion is heated from 80 to 92 C. Thus the unusual rheological character-istics of lOGT persist even when the dispersion is di-luted with Newtonian cross-linker and reactive diluent.
These characteristics indicate that the dispersion could be applied as a solventless coating at temperatures of 74 to 80 c. with commercial equipment capable of applying coatings at viscosities in the range of 0.5 - 0.7 Pa's and would resist sagging when heated at least to 92 C.
Alternatively, it could be applied at 92 C. with equip-ment capable of applying coatings at a viscosity of about 0.3 Pa-s at shear rates above about 3,000 sec~ and would resist sagging because of its shear thinning character-istics. Thus the unusual theological characteristics are exemplified in the following Tables.

WO 92/16~88 P~r/US92/0215 TABLE V.
The viscosities of 6aT blen~ th ~7~7 a~
~188 tr~tio 1:1:1 by ~reight).
_ ~
St~ Rbd~ T. 101.4-C. T - ~eLO'C. T - 7~LOrG T ~ 6110-G T- 51l0'G ll 25200 0.11 22680 0.11 0.24 _ 20160 0.11 0.23 ~
17640 0.11 0.23 . .
. . _ _ 15120 0.11 0.24 12600 0.11 0.24 _ 11340 0.11 0.25 0.49 10080 _ 0.11 0.25 0.48 8820 0.11 0.25 0.48 .' 1 5 7560 0.11 0.25 __ 0.47 6300 0.10 0.25 0.46 5040 0.13 0.31 0.58 4536 0.13 0.31 0.57 1.20 4032 0.12 0.31 O.S7 1.20 2 0 352a 0.12 0.32 0.57 1.21 1.50 3024 0.12 0.32 0.59 121 1.46 2016 0.18 0.41 0.85 1.49 1.96 1814 0.18 0.~1 0.85 1.52 1.96 1613 0.19 0.43 0.87 1.56 1.96 2 5 1411 0.20 0.4S 0.89 1.54 1.95 1209.9 0.20 0.45 . 0'95_ 1 Q 1'99 * The viscosity is too high to bc measurablc by HAA~OE viscomcter.

w092/~6588 ,~ g PCT/US92/0215 TAB~E VI
T~e viscosities of ~188 blo~ded wit~ 6GT
(ratio l:l by ~-~ght).
. . , ..-. ~
~ ~ ~ ) ~-1) T- T~ T- T- T- T~ T=
1064-C~.l-C ~-C 79D-C 7slrc ~C c~o-C ¦
2s200 0.080.14 0.20 =
22680 0.080.14 021 _ 20160 0.090.15 0.21 0.28 17640 0.090.15 0.21 0.28 15120 0.090.15 0.21 0.28 ~ _ 26000.080.150.21 0.28 11340 0.0~0.15 0.21 028 O.~B
10080 O.o70.14 0.21 025 0.~8 . .
88200.070.140.21 0.24 0.
7560o.o70.130.20 0.24 0.49 . .
.
63000.060.130.19 O.S0 50400.110.170.2s 0.34 0.5 45360.-110.160.25 0.34 O.S8 121 20 ~ o.1o 0.16 Q2s 0.3S 0.5 3s280.100.160.26 0.36 0.60 1.20 .
30240.100.150.26 037 0.62 1.20 20160.150.210.32 047 0.82 1.40 1.
18140.150.210.33 0.47 O.U 1.36 1.
16130.150.210.35 O.S0 O.Q~ 1.32 1.8~
~ o.15 0210.38 O.S5 0.90 1.30 1.95 1209.6 0.14 0.~ 0.38 05~ 0.96 1.1~ 1.94 * The viscosity is too 1~ to ~ e measur ble by H~ AKE viscc ~cter.
As shown in Tables V and VI, rheological behavior of dispersions of 6GT in Kl88 and in Kl88 and R747 is broad-ly similar to that of the dispersions of lOGT discussed above. In this case the temperature range of greatest shear thinning behavior is lower (70 to 83 C.), and the viscosity in the approximately Newtonian temperature range (50 to 60-C.) is correspondingly higher. The trough in the viscosity-temperature curve was detected.
The various features of this invention which ar~
believed new are set forth in the following claims.

Claims (42)

1. A dispersion comprising:
a polyester having the general formula or an adduct of the polyester having the general formula HO-V-Al'-(W-Ar-X-Al-Y)? -Ar'-Z-OH
wherein V= -?- or a covalent bond;
Al' = (CH2)n or a covalent bond;

W= -?O-, -O?- or a covalent bond;

Ar = , or ;

X = -?O- or -O?- ;
Al = (CH2)n ;
Y = -?O- , -O?- or a covalent bond, but if X = -O-?- and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =

-?O-;
Ar' = or a covalent bond; and Z = -?- or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, ? ? 2 n = 2 to 20, and a cross-linking agent reactive with the polyester or adduct thereof in an amount effective for cross-linking the polyester to provide a coating binder having a pencil hardness of at least about 3H and a reverse impact resistance of at least about 60 inch-lbs.
at a binder thickness of about 1 mil.

2. A dispersion as recited in Claim 1 wherein the dispersion includes a solvent selected from the group consisting of water and an organic solvent.

3. A dispersion as recited in Claim 2 wherein the solvent is water and the adduct of the polyester is an amine salt.

4. A dispersion as recited in Claims 1 or 2 wherein the adduct of the polyester is the reaction product of the acid terminated polyester of the general formula and a mono-oxirane.

5. A dispersion as recited in Claim 4 wherein the adduct of the polyester is a modified polyester comprising at least about 10 weight percent of a radical from a mono-oxirane having not more than 25 carbon atoms which has been grafted onto the polyester.

6. A dispersion as recited in Claims 1 or 2 wherein the polyester is the reaction product of an arylene monomer selected from the group consisting of and mixtures thereof and a straight chain saturated aliphatic diol or diacid having 6 to 17 carbon atoms which diol or diacid is reactive with the arylene monomer and wherein R = alkyl having 1 to 4 carbon atoms or H, R' = alkyl having 1 to 4 carbon atoms and X = halogen.

7. A dispersion as recited in Claims 1 or 2 wherein the polyester has the general formula

8. A dispersion as recited in Claims 1 or 2 wherein the polyester has the general formula

9. A dispersion as recited in Claims 1 or 2 wherein the polyester of the general formula is a hydroxyl terminated polyester, the hydroxyl terminated polyester being reacted with a polycarboxylic acid to provide a carboxylated polyester, the carboxylated polyester being reacted with a mono-oxirane to provide the adduct of the polyester of the general formula.

10. A polymeric vehicle which is dispersible in an organic solvent which polymeric vehicle when applied to a substrate provides a coating binder, the polymeric vehicle comprising:

a modified polyester and a cross-linking agent reactive with the modified polyester, wherein the modified polyester is the reaction product of a mono-oxirane having not more than 25 carbon atoms and an acid terminated polyester having a general formula HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= -?- or a covalent bond;
Al' = (CH2)n or a covalent bond;

W= -?O-, -O?- or a covalent bond;

Ar = , or X = -?O- or -O?-Al = (CH2)n Y = -?O- , -O?- or a covalent bond, but if X = -O-?- and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =
;

Ar' = or a covalent bond; ond Z = -?- or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, ? ? 2 n = 2 to 20, or the modified polyester is the reaction product of the mono-oxirane and a hydroxyl terminated polyester which has been carboxylated, the hydroxyl terminated polyester having hydroxyl functionality and the general formula.

11. A polymeric vehicle as recited in Claim 10 wherein the polyester is a hydroxyl terminated polyester which has the general formula and wherein the hydroxyl terminated polyester has been carboxylated to an acid value of from about 5 to about 230 before it is reacted with the mono-oxirane.

12. A polymeric vehicle as recited in Claim 10 wherein the polyester is a hydroxyl terminated polyester which has the general formula and wherein the hydroxyl terminated polyester has been carboxylated to an acid value of from about 5 to about 230 before it is reacted with the mono-oxirane.

13. A polymeric vehicle as recited in Claim 10 wherein the polyester has the general formula

14. A polymeric vehicle as recited in Claims 10 wherein the polyester has the general formula

15. A polymeric vehicle as recited in Claims 10, 11, 12, 13 or 14 wherein the modified polymer comprises at least about 10 weight percent of the radical from the oxirane.

16. A polymeric vehicle as recited in Claim 15 wherein the polyester of the general formula is the reaction product of an arylene monomer selected from the group consisting of hydroquinone, and mixtures thereof and a straight chain saturated aliphatic diol or diacid having 6 to 17 carbon atoms which diol or diacid is reactive with the arylene monomer and wherein R = alkyl having 1 to 4 carbon atoms or H, R' = alkyl having 1 to 4 carbon atoms and X = halogen.

17. A polymeric vehicle as recited in Claim 10 further comprising a polyester of the general formula, the modified polymer comprising at least about 70 weight percent of the polymers in the polymeric vehicle.

18. A polymeric vehicle which when applied to a substrate provides a coating binder, the polymeric vehicle comprising:
a blend of a polyester having the general formula HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= -?- or a covalent bond;
Al' = (CH2)n or a covalent bond:

W= -?O-, -O?- or a covalent bond;

A? = or ;
' X = -?O- or -O?- ;
Al = (CH2)n ;

Y = -?O- , -O?- or a covalent bond, but if X = -O-?- and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =

-O?- ;
Ar' = or a covalent bond; and z = -?- or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20, a cross-linking agent; and a modified polyester, and wherein the modified polyester is the reaction product of the polyester of the general formula with a mono-oxirane having not more than 25 carbons, the polyester of the general formula being reacted with a polyfunctional carboxylic acid to carboxylate the polyester of the general formula when the general formula is a diol prior to reacting the polyester of the general formula with the oxirane, the modified polyester in an amount in the blend which is effective for making the blend dispersible in an organic solvent.

19. A polymeric vehicle as recited in Claim 18 wherein the diol of the general formula is reacted with less than the stoichiometric amount of polyfunctional carboxylic acid.

20. A dispersion which when applied to a substrate provides a coating binder, the dispersion comprising:
a blend of a diol polyester having the general formula HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= -?- or a covalent bond:

Al' = (CH2)n or a covalent bond;

W= -?O-, -O?- or a covalent bond;

Ar = or X = -?O- or -O?- ;

Al = (CH2)n ;

Y = -?O- , -O?- or a covalent bond, but if X = -O-?- and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =
-?O-;
Ar' = or a covalent bond; and Z = -?- or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20, a cross-linking agent; and a reactive diluent, the reactive diluent being a hydrocarbon liquid having a viscosity in the range of from about 0.5 Pa?s to about 25 Pa?s and having about 1 to about 5 functional groups which are reactive with aminoplasts and isocyanates.

21. A dispersion as recited in Claim 20 which further includes an organic solvent.

22. A dispersion as recited in Claims 20 or 21 which further includes a dispersant, the reactive diluent and the reactive diluent being in amounts effective to disperse the polyester and the cross-linking agent.

23. A polymeric vehicle as recited in Claim 20 wherein the reactive diluent is selected from the group consisting of an aromatic acid reaction product, a cyclohexyl reaction product and mixtures thereof, the aromatic acid reaction product comprising the reaction product of an aromatic acid and a mono-oxirane, the aromatic acid selected from the group consisting of terephthalic acid, parahydroxy benzoic acid and 2,6-naphthalenic acid and the mono-oxirane having not more than 25 carbon atoms, the cyclohexyl reaction product comprising the reaction product of a cyclohexyl composition and the mono-oxirane, the cyclohexyl composition comprising the reaction product of a straight chain aliphatic diacid having 4 to 14 carbon atoms with 1,4-dimethylol cyclohexane or the cyclohexyl composition comprising the reaction product of 1,6-cyclohexane dicarboxylic acid with a straight chain aliphatic diol having 4 to 14 carbon atoms.

24. A polymeric vehicle as recited in Claim 23 where the reactive diluent is the reaction product of terephthalic acid and the mono-oxirane.

25. A polymeric vehicle as recited in Claim 23 wherein the reactive diluent is a cyclohexyl reaction product and the cyclohexyl composition is the reaction product of a diacid having 4 to 14 carbon atoms with 1,4-dimethylol cyclohexane.

26. A polymeric vehicle as recited in Claims 23, 24 or 25 wherein the polyester to diluent ratio in the blend are in the range of from about 10:1 to about 1:4.

27. A polymeric vehicle as recited in Claims 23 or 21 wherein the polyester has the general formula

28. A polymeric vehicle as recited in Claims 23 or 21 wherein the polyester has the general formula

29. A polymeric vehicle as recited in Claim 27 wherein the polyester to diluent ratio is in the range of from about 4:1 to about 1:4.

30. A polymeric vehicle as recited in Claim 28 wherein the polyester to diluent ratio is in the range of from about 4:1 to about 1:4.

31. A water dispersible polymeric vehicle which when applied to a substrate provides a coating binder, the polymeric vehicle comprising the amine salt of a polyester having an acid value of at least about 30 and which has the general formula HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= -C- or a covalent bond;
Al' = (CH2)n or a covalent bond;

W= -?O-, -O?- or a covalent bond:

Ar = , or X = -?O- or -O?- ;
Al = (CH2)n ;

Y = - ?O- , -O?- or a covalent bond, but if X = -O-?- and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =

-?O- ;
Ar' = or a covalent bond; and Z = -?- or a covalent bond wherein m-= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20, and the polyester of the general formula being reacted with a polyfunctional acid to carboxylate the polyester of the general formula when the general formula is a diol and to bring the acid value of the polyester to at least about 30.

32. A method of imparting liquid crystalline properties to a coating binder from a cross-linkable polymeric vehicle in an aqueous or organic solvent system for improved impact resistance and hardness of the coating binder, the method comprising:

dispersing a polyester with the polymeric vehicle, the polyester having the general formula or an adduct of the polyester HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= -?- or a covalent bond;
Al' = (CH2)n or a covalent bond:

W= -?O-, -O?- or a covalent bond;

Ar = , or X = -?O- or -O?- ;
Al = (CH2)n ;

Y = - ?O- , -O?- or a covalent bond, but if X = -O-?- and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =
-?O-;

Ar' = or a covalent bond;ond Z = -?- or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m > 2 n = 2 to 20, to provide a dispersion, the polyester or adduct thereof being in an amount effective to provide a coating binder with a pencil hardness of at least about 3H and a reverse impact resistance of at least about 60 inch-lbs. at a binder thickness of about 1 mil.

33. A method of providing a polymeric vehicle which has a viscosity which increases when the temperature of the polymeric vehicle is increased above about 25 C., the polymeric vehicle comprising oligomers having a number average molecular weight not greater than about 10,000, the method comprising dispersing at least one oligomer having a number average molecular weight not greater than about 10,000 with a composition of the general formula or an adduct of the composition to provide the polymeric vehicle HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= -?- or a covalent bond;
Al' = (CH2)n or a covalent bond;

W= -?O-, -O?- or a covalent bond;

Ar = , or X = -?O- or -O?- ;
Al = (CH2)n ;

Y = - ?O- , -O?- or a covalent bond, but if X = -O-?- and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =
-?O-;
Ar' = or a covalent bond; and Z = -?- or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20, and the polymeric vehicle comprising the composition of the general formula in an amount effective for the increase in the viscosity.

34. A method for increasing the shear thinning of a polymeric vehicle substantially free of polymers having a number average molecular weight of more than about 10,000 at about 25 C., the method comprising:
dispersing the polymeric vehicle with a composition of the general formula or an adduct of the composition to provide a modified polymeric vehicle, HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= -?- or a covalent bond;

Al' = (CH2)n or a covalent bond;

W= -?O-, -O?- or a covalent bond;

Ar = , or ;

X = or ;
Al = (CHz)n ;

Y = , or a covalent bond, but if X = and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =
;

Ar' = or a covalent bond; and Z = or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20, and the modified polymeric vehicle comprising the composition of the general formula or an adduct of the composition in an amount effective for the increase of shear thinning of the polymeric vehicle.

35. A method as recited in Claim 34 wherein the composition of the general formula or an adduct of the composition is in an amount effective for providing the modified polymeric vehicle with a viscosity of not more than about 5 Pa?s at a shear rate of at least about 3,000 sec-1 at about 25°C.

36. A method of increasing the viscosity of a polymeric vehicle when the temperature of the polymeric vehicle is increased above 25°C. and increasing the shear thinning of the polymeric vehicle at about 25°C., the polymeric vehicle being substantially free of polymers having a number average molecular weight greater than about 10,000, the method comprising dispersing the polymeric vehicle with a compound of the general formula or an adduct of the composition to provide a modified polymeric vehicle HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= or a covalent bond;
Al' = (CH2)n or a covalent bond;
W= , or a covalent bond;

Ar = , or X = or ;
Al = (CH2)n ;

Y = , or a covalent bond, but if X = and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =
;
Ar' = or a covalent bond; and Z = or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20, and the modified polymeric vehicle comprising the composition of the general formula or an adduct of the composition in an amount effective for providing the modified polymeric vehicle with a viscosity of not more than about 5 Pa?s at a shear rate of at least about 3,000 sec-1 at about 25°C.
and to increase the viscosity of the modified polymeric vehicle when the temperature of the modified polymeric vehicle in increased about 25°C.

37. A method for providing a polymeric vehicle which may be applied without mixing the polymeric vehicle with an aqueous or organic solvent, the polymeric vehicle having a viscosity of not more than about 5 Pa?s at a shear rate of at least about 3,000 sec-1 at a temperature in the range of from about 25°C. to about 100°C., the polymeric vehicle being substantially free of polymers having a number average molecular weight greater than about 10,000, the method comprising dispersing the polyester of the general formula or an adduct of the polyester of the general formula with a cross-linking agent, the general formula being HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= or a covalent bond;
Al' = (CH2)n or a covalent bond;

W= , or a covalent bond;

Ar = , or ;

X = or ;

Al = (CH2)n ;

Y = , or a covalent bond, but if X = and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =

;
Ar' = or a covalent bond; and Z = or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20.

38. The method as recited in Claim 37 further comprising dispersing a second oligomer with the cross-linking agent and the polyester of the general formula or an adduct of the polyester of the general formula to provide the polymeric vehicle.

39. An oxirane adduct of a diacid polyester having the general formula HO-V-Al'-(W-Ar-X-Al-Y)m -Ar'-Z-OH
wherein V= or a covalent bond;
Al' = (CH2)n or a covalent bond;

W= , or a covalent bond;

Ar = or ;

X = or ;
Al = (CH2)n ;

Y = , or a covalent bond, but if X = and if V = bond, and if Al' = bond, and if W = bond and if Z = bond, then Y =

;
Ar' = or a covalent bond; and Z = or a covalent bond wherein m= 1 to 20, but when V = bond, Al' = bond, W = bond and Z = bond, m ? 2 n = 2 to 20 or an oxirane adduct of a carboxylated diol polyester of the general formula.

40. An oxirane adduct as recited in Claim 34 wherein the oxirane is a mono-oxirane having not more than 25 carbon atoms.

41. An oxirane adduct as recited in Claim 40 wherein the polyester is a diacid polyester.

42. An oxirane adduct as recited in Claim 40 wherein the polyester is a carboxylated diol polyester.