Abstract:
Copolymers of an (ethylenedioxy)bis benzoate, an alkylene diol and a (2-alkenyl or alkyl) succinic anhydride, as well as surgical devices formed therefrom; especially, flexible monofilament surgical sutures having unique handling and knot-tying characteristics.

Description:
BACKGROUND OF THE INVENTION 
     The present invention relates to poly[alkylene-4,4&#39;-(ethylenedioxy)bis benzoate] copolymers as well as surgical devices formed therefrom. More particularly, this invention relates to flexible monofilament surgical sutures having unique handling and knot-tying characteristics. 
     Many natural and synthetic materials are presently used as surgical sutures. These materials may be used as single filament strands, i.e. monofilament sutures, or as multifilament strands in a braided, twisted or other multifilament construction. Natural materials such as silk, cotton, linen, and the like, do not lend themselves to the fabrication of monofilament sutures and are accordingly used mostly in one of the multifilament constructions. 
     Certain synthetic materials which are extruded in continuous lengths can be used in monofilament form. Common synthetic monofilament sutures include polypropylene, polyethylene and nylon 6. Such monofilament sutures are preferred by surgeons for many surgical applications due to their inherent smoothness and noncapillarity to body fluids. 
     Available synthetic monofilament sutures all suffer to a greater or lesser degree from one particular disadvantage, that is relative stiffness. Besides making the material more difficult to handle and use, suture stiffness or low compliance can adversely affect knot-tying ability and knot security. It is because of the inherent stiffness of available monofilament sutures that many suture materials are braided or have other multifilament constructions with better handling, flexibility and conformity. 
     Most monofilament sutures of the prior art are also characterized by a high degree of stiffness. This makes knot-tying difficult and reduces knot security. In addition, the low compliance and limited ductility prevent the suture from &#34;giving&#34; as a newly sutured wound swells, with the result that the suture may place the wound tissue under greater tension than is desirable, and may even cause some tearing, cutting or necrosis of the tissue. 
     The problems associated with the use of low compliance sutures in certain applications were recognized in U.S. Pat. No. 3,454,011, where it was proposed to fabricate a surgical suture composed of Spandex polyurethane. Such sutures, however, were too elastic and did not find general acceptance in the medical profession. 
     Recently issued U.S. Pat. No. 4,224,946 describes a monofilament suture with good flexibility and knot strength, which suture is composed of segmented polyetheresters which contain (1) a polymeric block of polyalkylene ethers and (2) a polymeric block of aromatic dicarboxylic acids or cycloaliphatic acids with short chain aliphatic or cycloaliphatic diols. Similar subject matter is disclosed in Belgian Pat. No. 880,486. 
     The ethylene glycol polyester of the subject diacid moiety, 4,4&#39;-(ethylenedioxy)bis benzoic acid, has been known for some time, (C.A. Registry No. [24980-45-8] if prepared from the acid, [26373-72-8] if prepared from the dimethyl ester) and, in fact, its ethylene glycol/polytetramethylene oxide copolymers (C.A. Registry Nos. [9071-04-9] and [51884-53-8] have been prepared: 
     CA 76 114610y 
     CA 80 83814u mentioned in index only 
     CA 81 171028s 
     CA 81 P12175g 
     CA 83 P195002w manufacture of elastic fiber 
     CA 84 P75556d polyester composite fibers with rubber-like elasticity) 
     as well as copolymers based on polyethylene oxide. These polyesters have been described as possessing improved crimpability, dyeability, and moisture absorption properties. 
     The 1,4-butanediol polyester of the subject diacid moiety is disclosed in Chemical Abstracts [52826-06-9]. In a 1978 paper (C.A. 89 60077c) which relates to the transesterification of dimethyl esters of aromatic dicarboxy acids with α-hydro-ω-hydroxy poly(oxyethylene)s and α,ω-alkanediols, a polytetramethylene oxide/1,4-butanediol copolymer based on the subject diacid moiety was made. 
     In spite of the fact that several polyethers could be incorporated chemically to toughen and lower the modulus of related polyesters, it is generally accepted that linear thermoplastics possessing a high initial modulus are more difficult to modify to increase compliance. Fibers of the (all hard) homopolymers of the subject invention were found to possess moduli in excess of 1.5 million psi, which renders it unsuitable for producing monofilament sutures. Patents that relate to (2-alkenyl or alkyl)succinates are U.S. Pat. No. 3,542,737 and U.S. Pat. No. 3,890,279. None of these patents discloses the present copolymers or modifications thereof. 
     Theory and experience in the art of fiber chemistry predict that branching (such as that present in the instant copolymers) may inhibit fiber formation and will exert a deleterious effect on the tensile properties of any resulting fibers due to the inability of the unoriented branch to contribute to the load bearing capacity of the fiber; and by the stearic interference posed by the branch to chain alignment during fiber orientation. It is therefore surprising that strong fibers, in particular strong, flexible compliant fibers may be formed from the present copolymers with pendant hydrocarbon chains. As will be seen from Table 1, Example (i), homopolymers prepared from the 1,4-butanediol polyester of the subject diacid moiety, have a modulus of 1,678,000 psi. It is surprising that the modulus of certain of the copolymers of the present invention is reduced to only 64,000 psi. 
     It is an object of the present invention to provide a novel copolymer of poly(alkylene-4,4&#39;-(ethylenedioxy)bis benzoate) as well as surgical devices formed therefrom. It is a further object of the present invention to provide a novel flexible, thermoplastic monofilament suture or ligature of said copolymer, having a diameter of from about 0.1 to 50 mil and possessing unique and desirable physical properties. Yet a further object of the present invention is to provide a Cobalt 60 sterilizable monofilament with lower modulus, better hand and more desirable tie-down characteristics than those of monofilaments of polypropylene. It is a further object of this invention to provide a monofilament suture with a desirable degree of ductility to accommodate changing wound conditions. It is yet another object of this invention to provide a monofilament suture with the flexibility and knot-tying characteristics of a braided suture. These and other objects will be made apparent from the ensuing description and claims. 
     SUMMARY OF THE INVENTION 
     The present invention relates to a copolymer comprising a multiplicity of recurring A and B units having the following general formula: ##STR1## wherein x and y are numbers having average values such that the B units comprise from 1 to 55 weight percent of the copolymer, and the A units comprise the remainder, 
     n is 2 to 8, and 
     R represents a linear or branched alkyl or alkenyl radical with a chain length of 4 to 30 carbon atoms, or a mixture of such radicals with different chain lengths. 
     In accordance with an embodiment of the invention, n is 4 and R has a chain length of 14-18 carbon atoms, the copolymer having an inherent viscosity of between 0.5 and 2.2 and a melting temperature of between 100° and 200° C. Preferably B comprises from 20-40 weight percent of the copolymer. A preferred copolymer composition has an inherent viscosity of between 0.8 and 1.5, and a melting temperature of between 135° and 170° C. 
     The most preferred embodiments of this invention include those copolymers in which R is a hexadec-2-enyl group CH 2  CH═CH--(CH 2 ) 12  CH 3 , and the A and B units are present on about a 72/28 mole basis; and R being a mixture of tetradec-2-enyl and octadec-2-enyl groups, the latter two R groups being present in about a 50/50 ratio (molar), the A and B units being present on about a 72/28 mole basis. 
     The invention also comprises surgical devices (especially sutures and clips) formed from the copolymer. 
     A size 3/0 strand of a filament of the present invention, has the following combination of mechanical properties: 
     Knot strength--at least 20,000 psi 
     Tensile strength--at least 30,000 psi 
     Young&#39;s modulus--less than about 600,000 psi 
     Elongation--from about 20% to 80% 
     Monofilament sutures of the present invention (having a size 3/0 strand) are preferably characterized by the following combination of mechanical properties: 
     Knot strength--30,000 to 65,000 psi 
     Tensile strength--45,000 to 100,000 psi (more preferably 60,000 to 100,000 psi) 
     Young&#39;s modulus--75,000 to 600,000 psi (more preferably 75,000 to 250,000 psi) 
     Elongation--from 20% to 55% 
     Sutures possessing the above characteristics may be prepared by melt extrusion, forming a continuous filamentry strand, and drawing the extruded filament to obtain the desired suture properties. 
     Monofilament sutures having physical properties in accordance with the present invention are particularly useful in many surgical procedures where the suture is used to close a wound which may be subject to later swelling or change in position. The combination of low Young&#39;s modulus and moderate to high elongation provides the suture with an appreciable degree of ductility and high compliance under low applied force. As a result, the suture is able to &#34;give&#34; to accommodate swelling in the wound area. In addition, the ductility and high tensile strength of the suture allow the suture to stretch during knot tie-down so that the knot &#34;snugs down&#34; for improved tying ability and knot security with a more predictable and consistent knot geometry regardless of variations in suture tying technique or tension. 
     Within the scope of the present invention is a filament as described above having a surgical needle attached to at least one end and useful as a surgical suture. Also within the scope of the present invention is such a filament or surgical suture in a sterile condition, and in addition such filament or sterile suture, packaged in a sterile enclosure. Also within the scope of the present invention is a method of closing a wound by approximating and securing the wound tissue with a filament or surgical suture of the present invention. 
     As may be seen from the attached Table 1, the copolymers of the present invention may be melt extruded into filaments suitable for use as synthetic sutures which are compliant and yet strong. Table 1 compares the properties of fibers formed from the present copolymer with those formed from other polymers. Specifically, Example (i) is the homopolymer of the 1,4-butanediol polyester of the subject diacid moiety. The remaining copolymers listed in Table 1 are, in each case, copolymers of the 1,4-butanediol polyester of the subject diacid moiety, with different types of non-crystallizable chain sequences (a) (known as soft-segments) which are listed at the bottom of Table 1. It will be noted that the homopolymer of Example (i) gives rise to fibers possessing moduli in excess of 1.5 million psi. Copolymers based in part on dimer acids (4G-D) according to Example (iv) as well as copolymers based in part on polyether [Examples (ii) and (iii)] give rise to values between about 250,000 and 500,000 psi even though the weight percent of the &#34;soft&#34; non-crystallizable portion ranges from 20% to 30%. Indeed even a polymer made to contain 30 weight percent of tetramethylene-2-octadecenyl succinate (Example IX) gives rise to fibers exhibiting a 350,000 psi Young&#39;s modulus. Polymers of Examples I, II and X provide unexpected results. The copolymer of Example I which contains 30 weight percent tetramethylene-2-hexadecenyl succinate moieties and the copolymer of Example II in which the &#34;soft&#34; segment is based on a mixture of tetramethylene-2-tetradecenyl succinate and tetramethylene-2-octadecenyl succinate give rise to compliant yet relatively strong fibers. 
    
    
     DESCRIPTION OF THE PREFERRED EMBODIMENTS 
     The copolymers of the present invention are prepared by the polycondensation of a 4,4&#39;-(ethylenedioxy)bis benzoate (preferably the dimethyl ester); a diol (preferably 1,4-butanediol); and a (2-alkenyl or alkyl) succinic anhydride. A (2-alkenyl or alkyl) succinic acid or a suitable derivative, such as a dialkyl ester [for example, dimethyl(2-alkenyl or alkyl)succinate], may be substituted for the anhydride and, in addition, a mixture of more than one(2-alkenyl or alkyl) succinic anhydride may be used. The diacid, 4,4&#39;-(ethylenedioxy)bis benzoic acid, may be used instead of the corresponding ester. ##STR2## 
     The diacid 4,4&#39;-(ethylenedioxy)bis benzoic acid is prepared by reaction of 1,2-dihaloethane and p-hydroxybenzoic acid in the presence of a suitable base, the reaction being followed by acidification to produce the free acid (which, after purification, can be used in a direct polymerization). The dimethyl ester is prepared by Fisher esterification and purified by recrystallization from ethyl acetate. Alternatively, the diester can be prepared directly by the reaction of a 1,2-dihaloethane with methyl p-hydroxy benzoate, prepared in a nonaqueous medium in the presence of a suitable base. The dimethyl ester is used to prepare by polycondensation techniques the polyesters listed in Table 1. 
     The required diols are commercially available. The substituted succinic anhydrides can be prepared by the &#34;ene&#34; reaction of maleic anhydride and an olefin (preferably a terminal olefin): ##STR3## wherein R&#39; is alkyl. 
     In the instance wherein R is alkyl, rather than alkenyl, the reactant may be prepared by hydrogenation of the corresponding alkenyl-succinic anhydride. 
     The polymerization may be run in the absence or, preferably, in the presence of stabilizers such as hindered phenols, {e.g., Irganox 1098 sold by Ciba-Geigy [N,N&#39;-hexamethylene bis(3,5-ditertbutyl-4-hydroxy hydrocinnamide)]} or secondary aromatic amines, {e.g., Naugard 445 sold by Uniroyal [4,4&#39;-bis(α,α-dimethylbenzyl)diphenylamine]}. Acetates, oxides and alkoxides of numerous polyvalent metals may be employed as the catalyst such as, for example, zinc acetate, or magnesium acetate in combination with antimony oxide, or zinc acetate together with antimony acetate. However, the preferred catalyst for the polymerization is a mixture of about 0.04 to 0.1% (based on total charge weight) tetrabutyl orthotitanate and about 0.004 to 0.006% magnesium acetate. If a dyed product is desired, a compatible dye such as, for instance, D&amp;C Green No. 6, can be added to the polymer or monomer mixture in concentrations of up to 0.5% based on expected polymer yield. 
     The polymerization is run in two stages. In the first stage, run under nitrogen at temperatures ranging from about 160° to 250° C., polycondensation via transesterification and esterification occurs, resulting in lower molecular weight polymers and oligomers. These are converted to higher molecular weight materials in the subsequent step run at about 220° to 255° C., at pressures of less than 1 mm of mercury. The resulting polymers, exhibit inherent viscosities (measured at a 0.1 g/dl concentration in hexafluoroisopropyl alcohol at 25° C.) of 0.5 to 2.2, and crystallinity of about from 20% to 50%. The Tm of the polymers (by microscopy), depending on composition, varies from about 90° to 230° C. 
     A summary of polymer properties is set forth in Table 1. 
     The polymers are readily extruded in a ram-type extruder, as for an example an Instron Capillary Rheometer at about 10° to 70° C. above the resin Tm, depending on the polymer&#39;s molecular weight. The resulting extrudates can be drawn and the total draw ratio may vary from 3X to 7X. 
     The unique oriented fibers exhibit an unexpected combination of properties. For example, strands of about 6 to 8 mil diameter displayed knot strenghts of 23,000-37,000 psi, straight tensile strengths of 50,000-69,000 psi and a Young&#39;s modulus of less than 350,000 psi. Percent elongations range from 23% to 37%. 
     In summary, the polymers described lend themselves to ready extrusion and drawing to strong and supple fibers which are useful as high compliance &#34;ultra limp&#34; sutures. The fibers are Cobalt 60 sterilizable without significant change in properties (in contrast to polypropylene fibers) and retain their strength in aqueous biological environment (in contrast to nylon 6 fibers). 
     The present polymers may also be used to prepare solid products (molded or machined) such as clips. 
     GENERAL POLYMERIZATION PROCEDURE 
     The desired amounts of dimethyl 4,4&#39;-(ethylenedioxy)bis benzoate, a 2-alkenyl succinic anhydride (or an alkyl succinic anhydride), a 1.3 to 2.0 molar excess of an alkylene diol per mole of diacid moieties (benzoate plus anhydride) and a given stabilizer are placed under nitrogen into a dry reactor fitted with an efficient mechanical stirrer, a gas inlet tube and a takeoff head for distillation. The system is heated under nitrogen to 160° C. and stirring is begun. To the stirred reaction mixture the required amount of catalyst is added. (Alternatively, the catalyst may be added along with the other reagents at the start, if they are dry). The mixture is then stirred and heated under nitrogen for given time periods at 190° C. (2 to 4 hours) and 220° C. (1 to 3 hours). The temperature is subsequently raised to 230° to 255° C. and over a period of 0.4 to 0.7 hours, the pressure is reduced in the system to about 1 mm/Hg (preferably 0.05 mm to 0.1 mm). (Alternatively, after reaction under nitrogen, the mixture may be allowed to cool to room temperature, vacuum applied at a later date and the batch heated to the reaction temperature). Stirring and heating under the above conditions is continued to complete the polymerization. The endpoint is determined by either (a) estimating visually the attainment of maximum melt viscosity, (b) measuring inherent viscosity or melt indices of samples removed from the reaction vessel at intermediate time periods, or (c) using a calibrated torquemeter (attached to the stirrer of the reactor). 
     At the end of the polymerization cycle the molten polymer is extruded and pelletized (or slow cooled in the glass reactor, isolated and ground in a mill). The polymer is dried at 80° to 110° C. for 8 to 16 hours under reduced pressure. One alternate method of polymerization is set forth in U.S. Pat. No. 3,890,279. 
     GENERAL EXTRUSION PROCEDURE 
     Extrusion using the Instrom Capillary Rheometer produces an extrudate which upon drawing (3× to 7× ratio) yields fibers in the 7 to 13 ml diameter range. The polymers are packed in the extrusion chamber and extruded through a 40 mil die after a dwell time of 9 to 13 minutes at the extrusion temperature. The ram speed is 2 cm/minute. While extrusion temperatures depend both on the polymer Tm and on the melt viscosity of the material at a given temperature, extrusion at temperatures of 10° to 70° C. above the Tm is usually satisfactory. The extrudate is taken up at a speed of about 18 to 24 feet per minute. 
     GENERAL DRAWING PROCEDURE 
     The extrudate (diameter range, 19-23 mils) is passed through rollers at an input speed of four feet per minute and then over a hot shoe or into a heated draw bath of glycerine. The temperatures of the hot shoe or draw bath vary from about 50° C. to 120° C. The draw ratio in this first stage of stretching varies from 3× to 6×. The drawn fibers are then placed over another set of rollers into a glycerine bath (second stage) kept at temperatures ranging from 60° C. to 100° C. Draw ratios of up to 2× are applied but usually only a slight amount of fiber extension (1.25×) is found desirable at this stage. Finally, the fiber is passed through a water wash, dried and taken up on a spool. 
     The copolymers of the present invention may be spun as multifilament yarn and woven or knitted to form sponges or gauze, (or nonwoven sheets may be prepared) or used in conjunction with other compressive structures as prosthetic devices within the body of a human or animal where it is desirable that the structure have high tensile strength and desirable levels of compliance and/or ductility. Useful embodiments include tubes, including branched tubes, for artery, vein or intestinal repair, nerve splicing, tendon splicing, sheets for tying up and supporting damaged kidney, liver and other abdominal organs, protecting damaged surface abrasions, particularly major abrasions, or areas where the skin and underlying tissues are damaged or surgically removed. 
     In more detail, the surgical and medical uses of the filaments of the present invention include, but are not necessarily limited to: 
     Knitted products, woven, or nonwoven including velours 
     a. burn dressings 
     b. hernia patches 
     c. medicated dressings 
     d. fascial substitutes 
     e. gauze, fabric, sheet, felt or sponge for liver hemostasis 
     f. gauze bandages 
     In combination with other components 
     a. arterial graft or substitutes 
     b. bandages for skin surfaces 
     c. burn dressings (in combination with polymeric films) 
     Solid products, molded or machined 
     a. orthopedic pins, clamps, screws and plates 
     b. clips 
     c. staples 
     d. hooks, buttons, and snaps 
     e. bone substitutes (e.g., mandible prosthesis) 
     f. needles 
     g. intrauterine devices 
     h. draining or testing tubes or capillaries 
     i. surgical instruments 
     j. vascular implants or supports 
     k. vertebal discs 
     l. Extracorporeal tubing for kidney and heart-lung machines 
     m. artificial skin and others. 
     
                                           TABLE 1__________________________________________________________________________Physical Properties of Fibers of Poly[tetramethylene-4,4&#39;-(ethylenedioxy)bis benzoate] and itsCorresponding Polyether, Dimerate and Alkenyl Succinate Copolymers            Example No.            (i)  (ii) (iii)                           (iv)                              I  II  VIII                                        IX X__________________________________________________________________________Type of non-crystallizable            None (b)                 PTMO--                      PTMO--                           4G--                              4G--                                 4G--                                     4G 4G 4Gchain segment (a)     EDBB EDBB D  S.sub.16                                 S.sub.14 /S.sub.18                                     S.sub.18                                        S.sub.18                                           S.sub.18Wt. % of non-crystallizable            0.00 20   30   25 30 14  25 30 40chain segment                         16Mole % of non-crystallizable            0.00 7    11   16 28 14  22 27 36chain segment                         14Polymer Inherent Viscosity,            1.40 1.70 1.13 0.99                              1.06                                 0.88                                     0.78                                        0.66                                           0.72dl/g (HFIP, 25° C., 0.1 g/dl)Polymer Tm (by   198  180  173  166                              150                                 150 158                                        163                                           150microscopy), °C.Extrusion Temperature, °C.            260  240  200  250                              200                                 200 240                                        175                                           185Drawing ConditionsOne Stage &#34;Hot-Shoe&#34;: Ratio            5X   5X   --   -- -- --  -- -- --Temp., °C.            101  101  --   -- -- --  -- -- --Multi-Stage Glycerin Draw Bath:1st Stage: Ratio --   --   5X   5X 5X 5X  5X 7X 5XTemp., °C.            --   --   53   55 55 52  55 58 502nd Stage: Ratio --   --   1.2X 1.3                              1.2X                                 1.2 1.3X                                        -- 1.2XTemp., °C.            --   --   70   70 70 70  75 -- 75Overall Draw Ratio            5X   5X   6X   6.5X                              6X 6X  6.5X                                        7X 6XPhysical Properties of FibersDiameter, mil    9.5  9.3  8.9  7.5                              7.7                                 7.9 6.6                                        6.5                                           8.1Straight Tensile Strength,            59   65   51   71 65 65  69 53 50psi × 10.sup.-3Knot Tensile Strength,            48   39   31   30 31 35  37 28 23psi × 10.sup.-3Elongation, %    27   45   42   24 31 36  26 23 37Modulus, psi × 10.sup.-3            1678 471  283  356                              166                                 140 314                                        350                                           64__________________________________________________________________________ (a) PTMO--EDBB = polytetramethylene oxide4,4(ethylenedioxy)bis 4G--D =  tetramethylene dimerate (from oleic acid dimerization) 4G--S.sub.16 = tetramethylene2-hexadecenylsuccinate (i.e. n = 4 and R = 2hexadecenyl) 4G--S.sub.14 = tetramethylene2-tetradecenylsuccinate (i.e. n = 4 and R = 2tetradecenyl) 4G--S.sub.18 = tetramethylene2-octadecenylsuccinate (i.e. n = 4 and R = 2octadecenyl) (b) The 1,4butanediol based homopolymer, poly[tetramethylene4,4(ethylenedioxy)bis benzoate] 
    
     The following are specific examples for producing new copolymers in accordance with the present invention. 
     EXAMPLE I 
     To a flame dried mechanically stirred, 100 ml two-neck glass reactor, suitable for polycondensation, is charged 19.60 g of dimethyl 4,4&#39;-(ethylenedioxy) bis benzoate (59.34 mmoles), 7.41 g of 2-hexadecenylsuccinic anhydride (23.0 mmoles), 14.83 g of 1,4-butanediol (164.6 mmoles), and 0.1510 g Erganox 1098 (0.5% of expected weight of formed polymer). 
     After purging the reactor and venting with nitrogen, the reactor is immersed in a silicone oil bath and connected to a gas supply to maintain nitrogen at 1 atmosphere of pressure. The stirred mixture is heated to 160° C.; the side neck is unstoppered and under a flush of nitrogen, 0.16 ml of an alcoholic tetrabutyl orthotitanate/magnesium acetate solution is carefully injected. (Preparation of catalyst solution: to 0.5000 g of anhydrous magnesium acetate is added 16.5 ml of methanol and 33 ml of a tetrabutyl titanate in n-butyl alcohol solution, previously prepared by mixing 12.3 ml of tetrabutyl titanate in 100 ml of n-butyl alcohol). After restoppering, the stirred mixture is heated to and maintained at 190°, 200°, and 220° C. for 1, 2, and 3 hours respectively, during which time the distillate is collected. The reactor is allowed to cool to room temperature. Some time later, the reactor is evacuated and heated to 150° C. to melt the reaction mass. Over the course of one hour, the temperature is slowly raised to 240° C. which is maintained for 6 hours. The collection of distillates is continued during the low pressure (less than 100 microns) stage of the polymerization. The reactor is removed from the oil bath and allowed to cool. The formed polymer is isolated, ground and then dried at 80° C. for 8 hours in vacuo. The polymer has an inherent viscosity of 1.06 dl/g as determined in hexafluoroisopropanol at 25° C. and a concentration of 0.1 g/dl. 
     EXAMPLES II TO X 
     A polymerization is carried out as described in Example I except that the reactor is charged with the ingredients listed in Table 2. The temperature at which the polymers melt is dependent on the composition so that in the transition from reaction under nitrogen to reaction under vacuum, a higher or lower temperature may have to be employed to melt the cooled reaction mass. 
     Table 3 lists the types of A and B units present in the copolymers obtained according to each of Examples I through X, as well as the weight and mole percent of each unit present in each copolymer. 
     
                                           TABLE 2__________________________________________________________________________Amount of DimethylExample4,4&#39;-(ethylenedioxy)           Anhydride        DiolNo.  bis benzoate (g)           Type       Amount (g)                            Type    Amount (g)__________________________________________________________________________I    19.60      2-hexadecenylsuccinic                      7.41  1,4-butanediol                                    14.83II   19.60      2-tetradecenylsuccinic                      3.38  1,4-butanediol                                    14.83           2-octadecenylsuccinic                      4.03III  19.60      2-butenylsuccinic                      6.17  1,4-butanediol                                    17.91IV   19.60      2-triacontenylsuccinic                      7.96  1,4-butanediol                                    13.46V    26.60      2-decenylsuccinic                      1.16  1,4-butanediol                                    15.39VI   14.00      2-hexadecenylsuccinic                      12.34 1,4-butanediol                                    14.54VII  21.28      2-hexadecenylsuccinic                      7.97  ethylene glycol                                    11.06VIII 21.00      2-octadecenylsuccinic                      6.26  1,4-butanediol                                    14.68IX   19.60      2-octadecenylsuccinic                      7.52  1,4-butanediol                                    14.56X    16.80      2-octadecenylsuccinic                      10.02 1,4-butanediol                                    14.32__________________________________________________________________________ In addition to the diester, the anhydride, and the diol, to each run is charged 0.1510 g of Erganox 1098 and 0.16 ml of a catalyst solution. Preparation of catalyst solution: to 0.5000 g of anhydrous magnesium acetate is added 16.5 ml of methanol and 33 ml of a tetrabutyl titanate i nbutyl alcohol solution, previously prepared by mixing 12.3 ml of tetrabutyl titanate in 100 ml of nbutyl alcohol. 
    
     
                                           TABLE 3__________________________________________________________________________Example                           Weight Percent                                     Mole PercentNo.  Type of A Unit          Type of B Unit     A   B   A   B__________________________________________________________________________I    Tetramethylene-4,4&#39;-          Tetramethylene-2-hexadecenylsuccinate                             70  30  72  28(ethylenedioxy)bisbenzoateII   Same as in I          Tetramethylene-2-tetradecenylsuccinate                             70  14  72  14          Tetramethylene-2-octadecenylsuccinate                                 16      14III  Same as in I          Tetramethylene-2-butenylsuccinate                             70  30  60  40IV   Same as in I          Tetramethylene-2-triacontenylsuccinate                             70  30  79  21V    Same as in I          Tetramethylene-2-decenylsuccinate                             95  5   94   6VI   Same as in I          Tetramethylene-2-hexadecenylsuccinate                             50  50  53  47VII  Ethylene-4,4&#39;-          Ethylene-2-hexadecenylsuccinate                             70  30  72  28(ethylenedioxy)bisbenzoateVIII Same as in I          Tetramethylene-2-octadecenylsuccinate                             75  25  78  22IX   Same as in I          Tetramethylene-2-octadecenylsuccinate                             70  30  73  27X    Same as in I          Tetramethylene-2-octadecenylsuccinate                             60  40  64  36__________________________________________________________________________ 
    
     EXAMPLE XI 
     Ten grams of the copolymer described in Example I are packed into the extrusion chamber of an Instron Rheometer equipped with a 40 mil die and, after 10 minutes of dwell time, the sample is extruded at a ram speed of 2 cm/minute, and a temperature of 200° C. The takeup speed of the extrudate is 18 ft/minute and the extrudate is quenched in ice water. The diameter of the extrudate is 19 to 23 mils. 
     The extrudate is drawn at 5× through a glycerine bath held at a temperature of 55° C. and at 1.2× through a second glycerine bath heated to 70° C. The resulting fiber is washed in a water bath (room temperature) to remove the glycerine and taken up on a spool. The total draw ratio for both the first and second drawing stage is 6×. Tensile data for fiber obtained by this and other extrusion and draw experiments are shown in Table 1.