# Patent

## Title
Pattern forming thermoplastic composition cores containing fluorescing

## Abstract

This is a continuation-in-part of application-in-part of application Ser. No. 274,293 filed on Jul. 12, 1994.

## Background
The present invention relates to a contact lens material having excellent transparency, high oxygen permeability and high heat resistance (high glass transition temperature), and moreover having excellent ultraviolet-ray absorbing property and excellent forming and processing property.

Conventionally, excellent oxygen permeability has been required for a contact lens as one of important physical properties because there is a necessity to supply a cornea with sufficient amount of oxygen through the contact lens so that functions of metabolism of corneal tissue would not be lowered.

Also, in order to avoid that bad influences owing to ultraviolet rays are exerted upon eyes, there has been proposed a contact lens in which an ultraviolet-ray absorbing agent is used. However, this contact lens has a problem in safety because the ultraviolet-ray absorbing agent easily elutes from the contact lens.

Accordingly, it is desired that an contact lens material which has transparency, improved oxygen permeability and heat resistance, and is excellent in ultraviolet-ray absorbing property is developed without using any ultraviolet-ray absorbing agent.

U.S. Pat. No. 5,049,156 and U.S. Pat. No. 4,955,900 disclose polyimides which are used in an intra-ocular lens. However, since the polyimides absorb not only ultraviolet rays but also visible rays, that is, rays having a wavelength of at least about 380 nm, the polyimides show bad transparency.

An object of the present invention is to provide a contact lens material having excellent transparency and high oxygen permeability.

Another object of the present invention is to provide a contact lens material having excellent forming and processing property as well as high heat resistance.

A further object of the present invention is to provide a contact lens material which efficiently absorbs ultra-violet rays having wavelengths of 320 to 280 nm (UV-B) and at most 280 nm (UV-C).

These and other objects of the present invention will become apparent from the description hereinafter.

In accordance with the present invention, there is provided a contact lens material comprising a condensation polymer having a recurring unit represented by the general formula (I): ##STR8## wherein R.sup.1 is --C(CF.sub.3).sub.2 -- or a group represented by the formula: ##STR9## R.sup.2 is a group represented by the general formula: ##STR10## in which l is an integer of 1 to 3, m is an integer of 1 to 15 and n is an integer of 1 to 3, a group represented by the general formula: ##STR11## in which u is an integer of 1 to 3 and v is an integer of 1 to 3, a group represented by the general formula (II): ##STR12## wherein R.sup.3, R.sup.4, R.sup.5 and R.sup.6 are the same or different and each is hydrogen atom or an alkyl group having 1 to 5 carbon atoms, or a group represented by the general formula (III): ##STR13## wherein R.sup.7 is --C(CF.sub.3).sub.2 --, a group represented by the formula: ##STR14## or a direct bond, and R.sup.8 and R.sup.9 are the same or different and each is an alkyl group having 1 to 3 carbon atoms, a fluoroalkyl group having 1 to 3 carbon atoms, hydrogen atom, hydroxyl group or carboxyl group.

The contact lens material of the present invention comprises, as mentioned above, a condensation polymer having a recurring unit represented by the general formula (I): ##STR15## wherein R.sup.1 is --C(CF.sub.3).sub.2 -- or a group represented by the formula: ##STR16## R.sup.2 is a group represented by the general formula: ##STR17## in which l is an integer of 1 to 3, m is an integer of 1 to 15 and n is an integer of 1 to 3, a group represented by the general formula: ##STR18## in which u is an integer of 1 to 3 and v is an integer of 1 to 3, a group represented by the general formula (II): ##STR19## wherein R.sup.3, R.sup.4, R.sup.5 and R.sup.6 are the same or different and each is hydrogen atom or an alkyl group having 1 to 5 carbon atoms, or a group represented by the general formula (III): ##STR20## wherein R.sup.7 is --C(CF.sub.3).sub.2 --, a group represented by the formula: ##STR21## or a direct bond, and R.sup.8 and R.sup.9 are the same or different and each is an alkyl group having 1 to 3 carbon atoms, a fluoroalkyl group having 1 to 3 carbon atoms, hydrogen atom, hydroxyl group or carboxyl group.

The above condensation polymer is prepared by the condensation polymerization of a monomer mixture comprising formula (IV): ##STR22## wherein R.sup.1 is the same as defined above, and (B) a diamino compound selected from formula (V): ##STR23## wherein l, m and n are the same as defined above, (b) a silicon-containing aromatic diamine represented by the general formula (VI): ##STR24## wherein u and v are the same as defined above, (c) a diamino-substituted benzene represented by the general formula (VII): ##STR25## wherein R.sup.3, R.sup.4, R.sup.5 and R.sup.6 are the same as defined above, and (VIII): ##STR26## wherein R.sup.7, R.sup.8 and R.sup.9 are the same as defined above.

The aromatic tetracarboxylic acid dianhydride represented by the general formula (IV) can be used alone.

In order to obtain a contact lens material which is more excellent in transparency, a compound represented by the general formula: ##STR27## is preferably used as the aromatic tetracarboxylic acid dianhydride.

As the silicon-containing diamine which is one of the diamino compounds, a silicon-containing aliphatic diamine represented by the general formula (V) is used.

As to the general formula (V), it is not preferable that each of l and n is an integer of more than 3 and that m is an integer of more than 15 because the shape stability of an obtained contact lens is apt to be lowered. It is preferable that m is an integer of 1 to 10.

Typical examples of the silicon-containing aliphatic diamine represented by the general formula (V) are, for instance, 1,3-bis(3-aminopropyl)-1,1,3,3-tetramethyldisiloxane, 1,3-bis(2-aminoethyl)-1,1,3,3-tetramethyldisiloxane, 1,3-bis(aminomethyl)-1,1,3,3-tetramethyldisiloxane, and the like, and they can be used alone.

As the silicon-containing diamine which is one of the diamino compounds, a silicon-containing aromatic diamine represented by the general formula (VI) is used.

As to the general formula (VI), it is not preferable that each of u and v is an integer of more than 3 because the shape stability of an obtained contact lens is apt to be lowered.

Typical examples of the silicon-containing aromatic diamine represented by the general formula (VI) are, for instance, 1,4-bis(3-aminopropyldimethylsilyl)benzene, and the like, and they can be used alone.

As the diamino-substituted benzene which is one of the diamino compounds, a compound represented by the general formula (VII) is used.

As to R.sup.3, R.sup.4, R.sup.5 and R.sup.6 in the general formula (VII), it is not preferable that the number of carbon atoms in an alkyl group is more than 5, because reactivity of the above-mentioned aromatic tetracarboxylic acid dianhydride with the diamino-substituted benzene becomes low and the condensation polymer having a sufficient weight average molecular weight is hardly obtained.

Typical examples of the diamino-substituted benzene are, for instance, 2,4-diamino-1,3,5-trimethylbenzene, 2,4-diamino-1,3,5-triethylbenzene, 2,4-diamino-1,3,5-tri-n-propylbenzene, 2,4-diamino-1,3,5-tri-i-propylbenzene, 3,5-diaminotoluene, 3,5-diamino-o-xylene, 2,5-diamino-m-xylene, and the like, and they can be used alone.

As the diamino-substituted diphenyl which is one of the diamino compounds, a compound represented by the general formula (VIII) is used.

As to R.sup.8 and R.sup.9 in the general formula (VIII), it is not preferable that each number of carbon atoms of an alkyl group and a fluoroalkyl group is more than 3, because reactivity of the above-mentioned aromatic tetracarboxylic acid dianhydride with the diamino-substituted diphenyl becomes low and the condensation polymer having a sufficient weight average molecular weight is hardly obtained.

Typical examples of the diamino-substituted diphenyl are, for instance, 2,2-bis(aminohydroxyphenyl)hexafluoropropane represented by the formula: ##STR28## such as 2,2-bis(3-amino-4-hydroxyphenyl)hexafluoropropane, 2,2-bis(aminomethylphenyl)hexafluoropropane represented by the formula: ##STR29## such as 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane, 2,2'-bis(trifluoromethyl)benzidine represented by the formula: ##STR30## 9,9-bis(4-aminophenyl)fluorene represented by the formula: ##STR31## 2,2-bis(3-amino-4-carboxyphenyl)hexafluoropropane, 2,2-bis(3-amino-4-ethylphenyl)hexafluoropropane, 2,2'-bis(trifluoroethyl)benzidine, a compound represented by the formula: ##STR32## and the like, and they can be used alone.

It is desired that the molar ratio of the aromatic tetracarboxylic acid dianhydride/the diamino compound is at least 30/70, preferably at least 40/60, more preferably at least 45/55, and that the molar ratio is at most 70/30, preferably at most 60/40, more preferably at most 55/45. When the molar ratio is less than the above lower limit and exceeds the above upper limit, there is a tendency that a weight average molecular weight of the obtained condensation polymer becomes low and sufficient strength would not be imparted to the contact lens material. Moreover, in the present invention, it is more preferable that the number of moles of the aromatic tetracarboxylic acid dianhydride is nearly equal to that of the diamino compound, and especially, the number of moles of the aromatic tetracarboxylic acid dianhydride is equal to that of the diamino compound from the viewpoint that the reaction of the aromatic tetracarboxylic acid dianhydride with the diamino compound is a condensation polymerization reaction.

As a method for preparing the condensation polymer (hereinafter also referred to as polyimide), which is used in the contact lens material of the present invention, from the aromatic tetracarboxylic acid dianhydride and the diamino compound, there can be cited, for instance, a method comprising polymerizing a monomer mixture comprising the aromatic tetracarboxylic acid dianhydride and the diamino compound in an organic polar solvent at a temperature of room temperature to 80.degree. C. to give a polyamide acid, charging a mold with the organic polar solvent solution of the polyamide acid to form a contact lens having a desired shape, and evaporating and removing the organic polar solvent from the contact lens in air or in an inert gas at a temperature of 50.degree. to 350.degree. C. under atmospheric pressure or reduced pressure, and at the same time dehydrating the polyamide acid for its ring-closure to give a polyimide; a method comprising adding a benzene solution of pyridine and acetic anhydride to the organic polar solvent solution of the polyamide acid to give a mixture, heating the mixture to remove the organic polar solvent from the mixture and conduct the mixture to imidation to give a polyimide; and the like.

Moreover, in the former method cited as a method for preparing the polyimide, it is also possible that the polyamide acid is isolated by reprecipitation and then the isolated polyamide acid is dehydrated for its ring-closure by heating or using an imidation agent to give a polyimide. Furthermore, it is possible that a solution, which is obtained after the preparation of the polyamide acid, is heated for its imidation in situ to a temperature of at least 100.degree. C. to give a precipitate from the solution and the precipitate is filtrated and washed to give a polyimide.

As the above organic polar solvent, an amide-type organic polar solvent such as N,N-dimethylformamide or N,N-dimethylacetamide can be preferably exemplified, and they can be used alone or in an admixture thereof. Moreover, among the organic polar solvents, a compound having a boiling point of at most 170.degree. C. such as N,N-dimethylacetamide can be more preferably used.

Also, the amide-type organic polar solvent such as N,N-dimethylacetoamide is particularly preferably used in the present invention because a resulting polyimide is not colored although a resulting polyimide is colored when N-methyl-2-pyrrolidone is used. The reason why the resulting polyimide is not colored is that the amide-type organic polar solvent is evaporated before its decomposition owing to its low boiling point when the polyamide acid solution is heated and the polyamide acid is dehydrated for ring-closure to give a polyimide.

It is preferable to avoid the use of N-methyl-2-pyrrolidone as the organic polar solvent. The reason is that, as mentioned above, N-methyl-2-pyrrolidone is partially decomposed when the polyamide acid solution is heated and the polyamide acid is dehydrated for ring-closure to give a polyimide and thereby the remained decomposition products show dark brown color and the resulting polyimide is colored yellow brown. However, when the polyamide acid is prepared by using N-methyl-2-pyrrolidone as a solvent for polymerization, and the resulting polyamide acid solution is added to a poor solvent for the polyamide acid such as water to reprecipitate the polyamide acid, and the imidation of the reprecipitated polyamide acid is carried out in the absence of the solvent for polymerization, or when the polyamide acid is re-dissolved in other preferred solvent to carry out the imidation of the polyamide acid, it is possible to remove an evil influence such that N-methyl-2-pyrrolidone is colored.

Moreover, when the above organic polar solvent is used, a solvent which does not lower transparency of a resulting polyimide such as a poor solvent such as ethanol, toluene, benzene or xylene, or a good solvent such as dioxane or tetrahydrofuran (hereinafter referred to as THF) can be used together with the organic polar solvent so long as solubility of the resulting polyamide acid is not lowered, and they can be used alone or in an admixture thereof. However, it is preferable that the amount of the solvent such as the poor solvent or the good solvent used together with the organic polar solvent is less than 50% by weight, more preferably at most 30% by weight, of the total amount of the organic polar solvent and the solvent such as the poor solvent or the good solvent, because when a large amount of the poor solvent and the good solvent is used, there is a tendency that a bad influence is exerted on the solubility of the resulting polyamide acid.

The condensation polymer (polyimide) prepared by the condensation polymerization of the aromatic tetracarboxylic acid dianhydride and the diamino compound can be used alone. It is preferable that the weight average molecular weight of the condensation polymer (polyimide) is about 10,000 to about 500,000. When the weight average molecular weight is less than the above lower limit, there is a tendency that film-forming property of the condensation polymer and strength of the formed film become low. On the other hand, when the weight average molecular weight exceeds the above upper limit, there is a tendency that forming and processing property of the condensation polymer becomes low.

In the contact lens material of the present invention, some other condensation polymers (polyimides) can be included as well as the condensation polymer (polyimide) prepared by the condensation polymerization of the aromatic tetracarboxylic acid dianhydride and the diamino compound so long as the obtained contact lens material does not become opaque or cloudy.

Typical examples of the other condensation polymers (polyimides) are, for instance, polyimides described in, for instance, Japanese Unexamined Patent Publication No. 226359/1988, No. 252159/1988, No. 204672/1989, No. 313058/1989, No. 222960/1991, No. 205050/1991 and No. 220210/1993, U.S. Pat. No. 4,955,900, U.S. Pat. No. 5,049,156 and U.S. Pat. No. 5,260,352, and the like, and they can be used alone or in an admixture thereof.

Representative example of the other condensation polymer is a condensation polymer having a recurring unit represented by the general formula (IX): ##STR33## wherein R.sup.10 is --C(CH.sub.3).sub.2 -- or --C(CF.sub.3).sub.2 --, R.sup.11 is --C(CH.sub.3).sub.2 --, --C(CF.sub.3).sub.2 -- or --SO.sub.2 --.

It is preferable that the contact lens material of the present invention contains the condensation polymer (polyimide) prepared by the condensation polymerization of the monomer mixture comprising the aromatic tetracarboxylic acid dianhydride and the diamino compound in a content of 15 to 100% by weight, more preferably 20 to 100% by weight. When the amount of the above condensation polymer contained in the contact lens material is too small, there is a tendency that improved effects such as the improvement of heat resistance, oxygen permeability, ultraviolet-ray absorbing property and the like become insufficient.

As a typical method for producing an contact lens by using the above polyimide, there can be cited, for instance, the following four kinds of methods, and the like.

The first method comprises the following steps.

The above-mentioned polyamide acid solution is spread on a mirror-finished plate such as a glass plate or a stainless steel plate in a prescribed thickness, the plate is gradually heated to a temperature of 100.degree. to 350.degree. C. and the polyamide acid is dehydrated for ring-closure and its imidation is carried out to give a polyimide film. The necessary sheets of the obtained polyimide films are overlapped one on another to give a plate for molding having a predetermined thickness and the obtained plate for molding is subjected to a heat compression molding at a temperature of 200.degree. to 500.degree. C. under a pressure of 0.5 to 10 t/cm.sup.2 for about 0.1 to about 10 hours to give a transparent molding of the polyimide. The obtained transparent molding is subjected to a mechanical process by means of an apparatus such as a cutting apparatus or a grinding apparatus to form a contact lens.

It is possible that the heating of the polyamide acid solution and the removing of the organic polar solvent from the solution are continuously carried out so as to dehydrate the polyamide acid for ring-closure and carry out its imidation. Moreover, it is possible that the polyamide acid solution is heated and the organic polar solvent is removed from the solution under reduced pressure in an atmosphere of an inert gas.

Also, as an another method for forming the above polyimide film, there can be cited, for instance, a method comprising spreading the polyamide acid solution on a glass plate, heating the plate at a temperature of 100.degree. to 150.degree. C. for about 30 to about 120 minutes to form a membrane, dipping the membrane in a benzene solution of pyridine and acetic anhydride to remove the solvent and conduct the polyamide acid to imidation, and forming the membrane into a polyimide film, and the like.

The second method comprises the following steps.

The polyamide acid solution is added to a poor solvent for the polyamide acid such as water or methanol to reprecipitate the polyamide acid, and the polyamide acid is collected. Then, the polyamide acid is dehydrated for ring-closure by heating at a temperature of 100.degree. to 350.degree. C., conducted to imidation and pulverized to give a powdered polyimide. The obtained powdered polyimide is subjected to a heat compression molding at a temperature of 200.degree. to 500.degree. C. under a pressure of 0.5 to 10 t/cm.sup.2 for about 0.1 to about 10 hours in the same manner as in the above first method to give a transparent molding of the polyimide. The obtained transparent molding of the polyimide is subjected to a mechanical process in the same manner as in the above first method to give a contact lens.

In the second method, as another method for preparing the polyimide in a state of powder, there can be cited, for instance, a method comprising heating the polyamide acid solution at a temperature of 100.degree. to 200.degree. C. with stirring, converting the polyamide acid to a polyimide and collecting the polyimide from the system as a precipitate, and the like. In this method, there is an advantage that it is possible to subject the polyimide to a heat compression molding only after washing and drying the polyimide.

The third method comprises directly producing a transparent molding of the polyimide from the polyamide acid not by subjecting a polyimide film or a powdered polyimide to a heat compression molding as in the above first method or the above second method but by subjecting an obtained transparent molding of the polyimide to a mechanical process in the same manner as in the above first method to give a contact lens.

When the conventional drying method is used, it is difficult to produce a homogeneous molding of the polyimide having a thickness of at least 150 .mu.m because it is impossible to prevent the polyamide acid solution from foaming during drying. However, since it is employed in the third method that the polyamide acid solution is allowed to stand for a long period of time under reduced pressure and the solution is heated from the inside by means of far infrared rays, microwave or the like, it is possible to prepare a molding of the polyimide having a thickness of at least 500 .mu.m without foaming. In other words, a homogeneous molding of the polyimide can be directly produced from the polyamide acid by means of far infrared rays, microwave or the like.

The fourth method comprises the following steps.

According to the fourth method, acetic anhydride, and pyridine or triethylamine are added to the polyamide acid solution, the polyamide acid contained in the solution is conducted to imidation to give a polyimide solution, and the obtained polyimide solution is added to a poor solvent for the polyimide such as water or methanol to reprecipitate the polyimide. The obtained polyimide is filtrated, washed and dried to give a powdered polyimide. Then, the obtained powdered polyimide is added to a good solvent for the polyimide to give a polyimide solution, and the polyimide solution is cast to give a polyimide film.

Furthermore, in the above-mentioned four methods, it is possible that at least two kinds of the moldings of the polyimide or the powdered polyimides are dissolved in the good solvent for the polyimide again to give a solution and the solution is cast to form a polyimide film.

In the above four methods, as a method for producing a contact lens by mechanically processing the molding of the polyimide, there can be cited, for instance, a method comprising grinding a curved surface of the molding of the polyimide in accordance with the fitting power of a contact lens to give a contact lens. When the polyimide film is formed, a contact lens can be produced by providing the inside of a mold having a shape corresponding to a contact lens with the polyimide film and molding the polyimide film. In this case, the obtained contact lens can be subjected to a mechanical finishing process if necessary.

The contact lens material of the present invention is more specifically described and explained by means of the following Examples. It is to be understood that the present invention is not limited to the Examples, and various changes and modifications may be made in the invention without departing from the spirit and scope thereof.

The atmosphere of a 500 ml separable flask equipped with a dropping funnel, a tube for introducing nitrogen gas, a mechanical stirrer and a calcium chloride cylinder was replaced with dried nitrogen gas.

The separable flask was charged with 22.2 g (0.05 mole) of diphenylhexafluoroisopropylidenetetracarboxylic acid dianhydride (hereinafter referred to as 6FDA) represented by the formula: ##STR34## and 70 g of N,N-dimethylacetamide (hereinafter referred to as DMAc). While stirring the mixture in the separable flask at room temperature, a mixed solution of 15.5 g (0.05 mole) of 1,4-bis(3-aminopropyldimethylsilyl)benzene represented by the formula: ##STR35## and 50 g of DMAc was added dropwise with the dropping funnel to the separable flask to give a polyamide acid solution.

To the polyamide acid solution, 30.6 g (0.3 mole) of acetic anhydride and 15.8 g (0.2 mole) of pyridine were added with stirring. Then, the mixture in the separable flask was stirred for about 10 hours to give a polyimide solution.

To a 5 l beaker, about 1 l of methanol was added as a poor solvent. While stirring the methanol with a stirrer, about a half amount of the polyimide solution (about 100 g) was added dropwise with the dropping funnel to the beaker to give a polyimide in a state of powder.

The powdered polyimide was filtrated with a Nutsche and pulverized with a pulverizer to give polyimide particles.

The polyimide particles were added to a 1 l beaker and washed with about 500 ml of methanol with stirring on a water bath at 50.degree. C. After 20 minutes passed, the polyimide particles were filtrated, washed once again and dried in a vacuum drier at 90.degree. C. to give a powdered polyimide.

A plate having a thickness of 4 mm was obtained by means of compression molding of the powdered polyimide.

Also, the powdered polyimide was dissolved in 1,4-dioxane. The resulting solution was spread on a glass plate to form a membrane. The membrane was heated at 90.degree. C. for about 16 hours under vacuum to dry and cooled to room temperature to give a film having a thickness of 0.2 mm.

As the physical properties of the powdered polyimide, the plate or the film, film-forming property, refractive index, glass transition temperature, oxygen permeability, weight average molecular weight and ray transmittance (visible-ray transmittance and ultraviolet-ray transmittance) were examined in accordance with the following methods. The results are shown in Table 1.

(A) Film-forming property

The powdered polyimide after drying was dissolved in 1, 4-dioxane. The resulting solution was cast on a glass plate to give a film. Transparency and strength of the obtained film were evaluated in accordance with the following criteria for evaluation.

[Criteria for evaluation] high strength are observed. and a little small strength are observed. formed.

(B) Refractive index

A test piece having a thickness of 4 mm was obtained from the plate. The refractive index (n.sup.25.sub.D) of the test piece was measured by means of a Abbe's refractometer commercially available from ATAGO CO., LTD. under the trade name of 1-T under the conditions that the temperature is 25.degree. C. and the relative humidity is 50%.

(C) Glass transition temperature

As an index of heat resistance, the glass transition temperature of the powdered polyimide was measured under the following conditions. Seiko Instruments Inc.

(D) Oxygen permeability

The film was cut and ground to give a test piece having a thickness of 0.2 mm. The oxygen permeability of the test piece dipped in a physiological saline at 35.degree. C. was measured by means of a Seikaken-type film oxygen-gas permeater commercially available from RIKASEIKI KOGYO CO., LTD.

The value of oxygen permeability listed on Table 1 means a value when the original value of the oxygen permeability is multiplied by 10.sup.11, and the unit of the value is ml (STP).multidot.cm/(cm.sup.2 .multidot.sec.multidot.mmHg).

(E) Weight average molecular weight

The weight average molecular weight of the powdered polyimide was measured under the following conditions. Co., Ltd.

The value of the weight average molecular weight listed on Table 1 means a value when the original value of the weight average molecular weight multiplied by 10.sup.-4.

(F) Ray transmittance

The film was cut and ground to give a test piece having a thickness of 0.2 mm. Using a UV-3100 automatic recording spectrophotometer commercially available from SHIMADZU CORPORATION, a ray having a region of wavelength from 780 to 190 nm was irradiated to the test piece dipped in distilled water at 20.degree. C. Each ray transmittance of a visible region (wavelength: 780 to 380 nm) and an ultraviolet region (wavelength: 340 nm) was measured.

A powdered polyimide, a plate and a film were obtained in the same manner as in Example 1 except that distilled water was used instead of methanol as a poor solvent and the remained half amount of the polyimide solution obtained in Example 1 (about 100 g) was added dropwise with the dropping funnel to the 5 l beaker to give a polyimide in a state of powder. The physical properties thereof were examined in the same manner as in Example 1. The results are shown in Table 1.

The atmosphere of a 500 ml separable flask equipped with a dropping funnel, a tube for introducing nitrogen gas, a mechanical stirrer and a calcium chloride cylinder was replaced with dried nitrogen gas.

The separable flask was charged with 22.2 g (0.05 mole) of 6FDA and 60 g of DMAc. While stirring the mixture in the separable flask at room temperature, a mixed solution of 12.5 g (0.05 mole) of 1,3-bis(3-aminopropyl)tetramethyldisiloxane represented by the formula: ##STR36## and 40 g of DMAc was added dropwise with the dropping funnel to the separable flask to give a polyamide acid solution.

To the polyamide acid solution, 30.6 g (0.3 mole) of acetic anhydride and 15.8 g (0.2 mole) of pyridine were added with stirring. Then, the mixture in the separable flask was stirred for about 10 hours to give a polyimide solution.

To a 5 l beaker, about 2 l of distilled water was added as a poor solvent. While stirring the distilled water with a stirrer, the polyimide solution was added dropwise with the dropping funnel to the beaker to give a polyimide in a state of powder.

The powdered polyimide was filtrated with a Nutsche and pulverized with a pulverizer to give polyimide particles.

The polyimide particles were added to a 1 l beaker and washed with about 500 ml of distilled water with stirring on a water bath at 50.degree. C. After 20 minutes passed, the polyimide particles were filtrated, washed once again and dried in a vacuum drier at 80.degree. C. to give a powdered polyimide.

The powdered polyimide was dissolved in 1,4-dioxane. The resulting solution was cast on a glass plate, and the glass plate was allowed to stand for a week to form a membrane. The membrane was heated with a vacuum drier at 80.degree. C. to give a film having a thickness of 0.2 mm.

As a result, the obtained film had a mechanical strength tolerable for grinding.

As the physical properties of the powdered polyimide or the film, film-forming property, glass transition temperature, oxygen permeability, weight average molecular weight and ray transmittance (visible-ray transmittance and ultraviolet-ray transmittance) were examined in the same manner as in Example 1. Also, refractive index and machinability were examined in accordance with the following methods. The results are shown in Table 1.

(G) Refractive index

The film was cut, and the cut films were laminated to give a test piece having a thickness of 4 mm. The refractive index (n.sup.25.sub.D) of the test piece was measured by means of a Abbe's refractometer commercially available from ATAGO CO., LTD. under the trade name of 1-T under the conditions that the temperature is 25.degree. C. and the relative humidity is 50%.

(H) Machinability

The film was cut, and the section thereof was observed with naked eyes. The machinability was evaluated in accordance with the following criteria for evaluation.

[Criteria for evaluation] the section.

There was used a polyimide mixture (I) of 30% by weight of a polyimide having a recurring unit represented by the formula: ##STR37## wherein R.sup.12 is a group represented by the formula: ##STR38## and 70% by weight of a polyimide having a recurring unit represented by the formula: ##STR39## wherein R.sup.13 is as defined above.

A 20% by weight ethylene glycol dimethyl ether solution of the polyimide mixture (I) was cast on a glass plate and allowed to stand for a week at room temperature to form a polyimide film having a thickness of about 2 mm.

The polyimide film was pulverized by a pulverizer to give a powdered polyimide.

The polyimide film was gouged out with a punch to give a film having a diameter of 15 mm, and the film was cut and ground so that its thickness could be 0.2 mm.

As the physical properties of the powdered polyimide or the film, film-forming property, refractive index, glass transition temperature, oxygen permeability, ray transmittance (visible-ray transmittance and ultraviolet-ray transmittance) and machinability were examined in the same manner as in Example 3. The results are shown in Table 1.

A film was obtained in the same manner as in Example 1 except that a polyimide mixture (II) of 30% by weight of a polyimide having a recurring unit represented by the formula: ##STR40## wherein R.sup.14 is a group represented by the formula: ##STR41## and 70% by weight of a polyimide having a recurring unit represented by the formula: ##STR42## wherein R.sup.14 is as defined above was used instead of the polyimide mixture (I).

The physical properties of the powdered polyimide or the film were examined in the same manner as in Example 4. The results are shown in Table 1.

The atmosphere of a 500 ml separable flask equipped with a dropping funnel, a tube for introducing nitrogen gas, a mechanical stirrer and a calcium chloride cylinder was replaced with dried nitrogen gas.

The separable flask was charged with 22.2 g (0.05 mole) of 6FDA and 70 g of DMAc. While stirring the mixture in the separable flask at room temperature, 7.5 g (0.05 mole) of 2,4-diamino-1,3,5-trimethylbenzene was added dropwise with the dropping funnel to the separable flask to give a polyamide acid solution.

To the polyamide acid solution, 26.8 g (0.26 mole) of acetic anhydride and 26.8 g (0.34 mole) of pyridine were added with stirring. Then, the mixture in the separable flask was stirred for about 24 hours to give a polyimide solution.

To a 5 l beaker, about 3.5 l of methanol was added as a poor solvent. While stirring the methanol with a stirrer, the polyimide solution was added dropwise with the dropping funnel to the beaker to give a polyimide in a state of powder.

The powdered polyimide was finely pulverized to give fine particles by means of a pulverizer, washed with a large amount of methanol and dried under vacuum at 150.degree. C. to give powdered polyimide.

The powdered polyimide was dissolved in 1,4-dioxane. The resulting solution was spread on a glass plate to form a membrane. The membrane was heated at 130.degree. C. for 16 hours under vacuum to dry and gradually cooled to room temperature to give a film having a thickness of 0.2 mm.

As the physical properties of the powdered polyimide or the film, film-forming property, oxygen permeability, weight average molecular weight and ray transmittance (visible-ray transmittance and ultraviolet-ray transmittance) were examined in the same manner as in Example 3. Also, glass transition temperature was measured in accordance with the following method. The results are shown in Table 1.

(I) Glass transition temperature

As an index of heat resistance, the glass transition temperature of the powdered polyimide was measured in accordance with the following conditions. from Rheometrics Far East LTD. under the trade name of RSA-II

A powdered polyimide and a film were obtained in the same manner as in Example 6 except that 8.9 g (0.02 mole) of 6FDA was used instead of 22.2 g, that 2.7 g (0.018 mole) of 2,4-diamino-1,3,5-trimethylbenzene was used instead of 7.5 g (0.05 mole) and that 1.8 g (0.002 mole) of a silicon-containing diamine represented by the formula: ##STR43## was added to the 2,4-diamino-1,3,5-trimethylbenzene. The physical properties thereof were examined in the same manner as in Example 6. The results are shown in Table 1.

The atmosphere of a 500 ml separable flask equipped with a dropping funnel, a tube for introducing nitrogen gas, a mechanical stirrer and a calcium chloride cylinder was replaced with dried nitrogen gas.

The separable flask was charged with 8.9 g (0.02 mole) of 6FDA and 48.5 g of DMAc. While stirring the mixture in the separable flask at room temperature, 7.3 g (0.02 mole) of 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane was added to the separable flask to give a polyamide acid solution.

To the polyamide acid solution, 10.7 g (0.11 mole) of acetic anhydride and 10.7 g (0.13 mole) of pyridine were added with stirring. Then, the mixture in the separable flask was stirred for about 24 hours to give a polyimide solution.

To a 1 l beaker, about 500 ml of methanol was added as a poor solvent. While stirring the methanol with a stirrer, the polyimide solution was added dropwise with the droppng funnel to the beaker to give a polyimide in a state of powder.

The powdered polyimide was finely pulverized to give fine particles, washed with a large amount of methanol and dried under vacuum at 80.degree. C. to give a powdered polyimide.

The powdered polyimide was dissolved in 1,4-dioxane. The resulting solution was spread on a glass plate to form a membrane. The membrane was heated at 70.degree. C. for 16 hours under vacuum to dry and gradually cooled to room temperature to give a film having a thickness of 0.2 mm.

As the physical properties of the powdered polyimide or the film, film-forming property, glass transition temperature, oxygen permeability, weight average molecular weight and ray transmittance (visible-ray transmittance and ultraviolet-ray transmittance) were measured in the same manner as in Example 6. Also, machinability was measured in the same manner as in Example 3. The results are shown in Table 1.

A powdered polyimide and a film having a thickness of 0.2 mm were obtained in the same manner as in Example 8 except that 7.3 g (0.02 mole) of 2,2-bis(3-amino-4-hydroxyphenyl)hexafluoropropane was used instead of 7.3 g (0.02 mole) of 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane. The physical properties thereof were examined in the same manner as in Example 8. The results are shown in Table 1.

A powdered polyimide and a film having a thickness of 0.2 mm were obtained in the same manner as in Example 8 except that 6.4 g (0.02 mole) of 2,2-bis(trifluoromethyl)benzidine was used instead of 7.3 g (0.02 mole) of 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane. The physical properties thereof were examined in the same manner as in Example 8. The results are shown in Table 1.

A powdered polyimide and a film having a thickness of 0.2 mm were obtained in the same manner as in Example 8 except that 7.0 g (0.02 mole) of 9,9-bis(4-aminophenyl)fluorene was used instead of 7.3 g (0.02 mole) of 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane. The physical properties thereof were examined in the same manner as in Example 8. The results are shown in Table 1.

A powdered polyimide and a film having a thickness of 0.2 mm were obtained in the same manner as in Example 8 except that 6.6 g (0.018 mole ) of 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane was used instead of 7.3 g (0.02 mole) and 1.8 g (0.002 mole) of a silicon-containing diamine represented by the formula: ##STR44## was added to the 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane. The physical properties thereof were examined in the same manner as in Example 8. The results are shown in Table 1.

A powdered polyimide and a film having a thickness of 0.2 mm were obtained in the same manner as in Example 8 except that 6.3 g (0.018 mole) of 9,9-bis(4-aminophenyl)fluorene was used instead of 7.3 g (0.02 mole) of 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane and 1.8 g (0.002 mole) of a silicon-containing diamine represented by the formula: ##STR45## was added to the 9,9-bis(4-aminophenyl)fluorene. The physical properties thereof were examined in the same manner as in Example 8. The results are shown in Table 1.

A powdered polyimide and a film having a thickness of 0.2 mm were obtained in the same manner as in Example 8 except that 5.8 g (0.016 mole) of 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane was used instead of 7.3 g (0.02 mole) and 1.2 g (0.004 mole) of a silicon-containing diamine represented by the formula: ##STR46## was added to the 2,2-bis(3-amino-4-methylphenyl)hexafluoropropane. The physical properties thereof were examined in the same manner as in Example 8. The results are shown in Table 1. __________________________________________________________________________ Physical properties of powdered polyimide, plate or film Glass         Weight transition    average Ray transmittance (%) Example Film-forming Refractive temperature Oxygen molecular Visible-ray Ultraviolet-ray Machin- No.  property index (-) (.degree.C.) permeability weight transmittance transmittance ability __________________________________________________________________________ 1    A      1.56  130    2      5.4   90.ltoreq. 0       -- 2    A      1.56  123    1.8    5.4   90.ltoreq. 0       -- 3    A      1.63  103    9.3    1.2   90.ltoreq. 0       A 4    A      1.54  120    23     --    85.ltoreq. 0       A 5    A      1.56  150    22     --    85.ltoreq. 0       A 6    A      --    410    30     9.8   90.ltoreq. 0       -- 7    A      --      200.ltoreq. 60     16    90.ltoreq. 0       -- 8    A      --    292    9      5.8   85.ltoreq. 0       B 9    A      --    263    2      4.0   85.ltoreq. 0       B 10   A      --    340    7      11.7  85.ltoreq. 0       B 11   A      --    392    9      7.7   85.ltoreq. 0       B 12   A      --    276    9      6.2   85.ltoreq. 0       A 13   A      --    354    12     5.8   85.ltoreq. 0       A 14   A      --    240    6      5.0   85.ltoreq. 0       A __________________________________________________________________________

Generally, polyimides have red brown color and opacity.

However, as is clear from the results of Examples 1 to 14 shown in Table 1, the polyimides obtained in these Examples have high visible-ray transmittance of at least 85% and are excellent in transparency and film-forming property because the aromatic tetracarboxylic acid dianhydride is used as a component of the present invention.

As is clear from the results shown in Table 1, the polyimides obtained in Examples 1 to 14 have high oxygen permeabity. The polyimides also have excellent forming and processing property because the polyimides have sufficient strength and high machinability. Furthermore, the polyimides have high glass transition temperature and excellent heat resistance.

Also, as is clear from the results shown in Table 1, the polyimides obtained in Examples 1 to 14 show ultraviolet-ray transmittance of 0% at the wavelength of 340 nm. However, the polyimides show visible-ray transmittance of at least 85% within the region of wavelength of 780 to 380 nm. Therefore, the cut-off point of ultraviolet-rays would be within the range of 340 to 380 nm.

Accordingly, since the polyimides obtained in Examples 1 to 14 have a specific recurring unit, the polyimides sufficiently transmit visible-rays and absorb ultraviolet-rays. In other words, the polyimides are excellent in transparency as well as ultraviolet-ray absorbing property within the wavelength of 320 to 280 nm (UV-B) and at most 280 nm (UV-C).

As explained in the above, the polyimides obtained in Examples 1 to 14 are desirable for a contact lens material.

Although the polyimides obtained in Examples 1 to 5 have a refractive index lower than usual polyimides, each of these polyimides has high refractive index suitable for a contact lens material since each of these polyimides contains a silicon atom in its molecule.

The polyimides obtained in Examples 6 to 14 especially have high glass transition temperature and excellent heat resistance because the diamino-substituted benzene and the diamino-substituted diphenyl are used as a diamino compound.

The contact lens material of the present invention is particularly excellent in oxygen permeability, heat resistance, ultraviolet-ray absorbing property and forming and processing property as well as transparency. Accordingly, the ocular lens materials of the present invention are particularly useful for contact lenses.

In addition to the ingredients used in the Examples, other ingredients can be used in the Examples as set forth in the specification to obtain substantially the same results.

## Claims

1. A contact lens material comprising a condensation polymer having a recurring unit represented by the general formula (I): ##STR47## wherein R.sup.1 is --C(CF.sub.3).sub.2 -- or a group represented by the formula: ##STR48## R.sup.2 is a group represented by the general formula: ##STR49## in which l is an integer of 1 to 3, m is an integer of 1 to 15 and n is an integer of 1 to 3, a group represented by the general formula: ##STR50## in which u is an integer of 1 to 3 and v is an integer of 1 to 3, a group represented by the general formula (II): ##STR51## wherein R.sup.3, R.sup.4, R.sup.5 and R.sup.6 are the same or different and each is hydrogen atom or an alkyl group having 1 to 5 carbon atoms, or a group represented by the general formula (III): ##STR52## wherein R.sup.7 is --C(CF.sub.3).sub.2 --, a group represented by the formula: ##STR53## or a direct bond, and R.sup.8 and R.sup.9 are the same or different and each is an alkyl group having 1 to 3 carbon atoms, a fluoroalkyl group having 1 to 3 carbon atoms, hydrogen atom, hydroxyl group or carboxyl group.

2. The contact lens material of claim 1, which contains said condensation polymer in a content of 15 to 100% by weight.

3. The contact lens material of claim 1, which contains said condensation polymer and a condensation polymer having a recurring unit represented by the general formula (IX): ##STR54## wherein R.sup.10 is --C(CH.sub.3).sub.2 -- or --C(CF.sub.3).sub.2 --, R.sup.11 is --C(CH.sub.3).sub.2 --, --C(CF.sub.3).sub.2 -- or --SO.sub.2 --.