STAR-SHAPED BRANCHED POLYAMIDE

Abstract: The invention relates to a star-shaped branched polyamide that has a high thermal stability and can be produced in existing production facilities for the corresponding linear polyamide. This is achieved by allowing the polyamide branches, at least three, to be formed from a multifunctional core having functional groups chosen from the group comprising amine and carboxyl groups, the amine or carboxyl groups being bound to an acyclic compound in which branching occurs, if it is branched, at a carbon atom, or via an acyclic chain to a heterocyclic compound showing point symmetry. The process for the preparation is carried out under the conditions of the preparation of the corresponding linear polyamide. It proves to be possible to obtain, after shorter polymerisation times, a product with mechanical properties that are comparable with those of the linear polyamide after significantly longer polymerisation times. Examples of suitable multifunctional nuclei are 2,4,6-trisaminocaproic acid-1,3,5-triazine and 4-aminomethyl-1,1-octanediamine.

Description: 9 - 1 - STAR-SHAPED BRANCHED POLYAMIDE The invention relates to a star-shaped branched polyamide with at least 3 polyamide branches, which is formed from a multifunctional nucleus having functional groups chosen from the group comprising amine and carboxyl groups, and a process for the preparation thereof, Such star-shaped branched polyamides are known from J.R. Schaefgen and P.J. Flory, J. Am. Chem. Soc. 70 . , 2709-18 (1948), which describes star-shaped branched polyamides whose branches are formed in the polymerisation of ε-caprolactam and cyclohexanone tetraproprionic acid. Examples of star-shaped branched polyamides whose branches are initiated by amine groups are described in J.M. ara o ski, Chem. Mater. 1992, 4, 1000-1004 (1992). Here a star-shaped branched polyamide is obtained in the polymerisation of ε-caprolactam on tris(2--aminoethyl)amine, N,N-bis(2-aminoethyl)-N', '- bis12-[bis(2-aminoethyl)aminoJethyl]-1,2-ethanediamine and the polyethylene i ine dendrimer of the following generation. The use of the aforemen ioned mul ifunctional core molecules however involves several drawbacks. It is not possible to obtain branches with high molecular weights using Flor 's carboxylic acid core molecules, and, at the postpolymerisation temperatures employed, molecular decomposition and crosslinking take place after some time and the fraction of linear polyamide increases. Warakomski 's amine polymerisation initiators present the drawback of slow polymerisation initiation. - 2 - There is a high risk of the formation of linear polyamide owing to contamina ions and the number of branches formed is difficult to control. One of the conditions in the preparation of the star-shaped branched polyamide according to this state of the art is the complete absence of water,,This necessitates long polyme isation times and extra measures in comparison with the usual polymerisation processes for ε-caprolactam to polyamide-6. For this reason Warakomski makes use of the hydrochlo ides of the amines. After the polymerisation these hydrochlorides must first be carefully removed, which means that extra operations and the necessary equipment are required. The aim of the invention is to provide a star-shaped branched polyamide which (a) can be obtained using the usual polyme isa ion processes for linear polyamides, which (b) can be obtained with a high degree of polymerisation which (c) shows no significant decomposition or croeslinking at the temperature at which the polyme isa ion process takes place and which (d) also shows a good stability with respect to processing in the melt. The inventors have now found that a star- shaped branched polyamide in which the amine or carboxyl groups of the core are bound (1) to an acyclic compound in which branching occurs, if it is branched, at a C atom or (2) via an acyclic chain to a heterocyclic compound meets the above requirements and hence does not show ox shows to only a small extent the drawbacks of the star- shaped branched polyamides according to the state of the art. Because the star-shaped branched polyamide according to the invention can be produced, without further investments, in existing polymerisation installations for the corresponding linear polyamide, an application in which use can be made of the low melt viscosity characteristic of star-shaped branched polyamides for, for example, injection-moulding thin- walled objects, has now come within reach. Suitable polyamides are polyamides of the so- called AB type, which can be obtained through polycondensation of α,w-amino acids or through ring- opening polyme isation of lactams. Examples are polyamide—4, polyamide-δ, polyamide-8, etcetera. Acyclic compounds are compounds having an open-chain molecular structure instead of a ring structure. Examples of such acyclic compounds are aliphatic hydrocarbons that are characterised by a straight or branched arrangement of the carbon atoms constituting the chain. Aliphatic hydrocarbons can be split up into alkanes, alkenes and acetylenes, which are saturated, unsaturated having a double bond, and unsaturated having a triple bond, respectively. In complex structures the chains may be branched o∑ crosslinked. Examples of such branched or crosslinked compounds are branched aliphatic compounds, for example 4-aminomethyl-l,8-octanediamine. If the branched or crosslinked compounds contain atoms other than carbon, chain branching occurs at the C atoms only. Preferably use is made of branched aliphatic compounds. The length of the main chain may then vary within a wide range, for example between 2 and 40 carbon atoms, and the length of the side chains may vary between 1 and 20 carbon atoms; preferably the main chain is chosen to be not longer than 20 carbon atoms and the side chains are not longer than 10 carbon atoms. The distance between the carbon atoms in the main chain to which branches are bound is preferably at least 2 carbon atoms. The amine or carboxyl group is preferably terminally bound to the aliphatic chains. In principle, there is no limit to the number of functional groups per main chain, but preferably the number of groups is limited to 3-10. The acyclic groups to which the initiator group is bound are preferably identical. The length of the acyclic chain to which the initiator group is bound is preferably chosen to be between l and 10 (carbon) atoms. If the chain is too short, there will be a risk of steric hindering, as a result of which it will not be possible for polyamide chains to be formed onto all the functional groups, whereas too long chains involve the risk of entanglement, which may hinder the formation of a regular star-shaped structure owing to shielding, among other factors. Heterocyclic compounds are compounds having a closed ring structure where one or more of the ring's atoms is an element other than carbon, for example sulphur, nitrogen or oxygen. Examples are pyridine, pyrroles, furans, thiophene and puxine. The heteroatoms present in the ring, however, affect the distribution of the electrons, as a result of which initiator groups bound to carbon atoms in the ring that are at different distances from heteroatoms have a different reactivity, which may result in irregular polymerisation initiation and the formation of irregular star-shaped branched polyamides. For this reason heterocyclic ring compounds showing point symmetry are particular suitable. Examples of such compounds are 1,3,5-triazines and 1,4 diazines, for example me1amine and compounds derived therefrom and 2,3,5,β-tβtraethylpyrazine, L,4- piperazines and tetrathiaphulvalenes. In principle there is no limit to the number of functional groups bound via acyclic chains per heterocyclic ring compound, but 3-10 groups per heterocyclic ring compound is preferred. The length of the acyclic chain to which the functional group is preferably terminally bound is preferably 1-10 atoms. The terminal functional group is preferably a carboxyl group. Preferably use is made of 2,4,6-t is- aminocaproic acid-1,3,5-triazine, in view of the simple and easily controllable way in which this compound can be obtained and the presence of aliphatic initiator groups that also correspond to the monomer for polyamide-6. Preferably one type of functional group is present per core molecule. The presence of - or the possibility of - the formation of different functional groups must preferably be avoided because of the implied possibility of crosslinking. The core molecule should be smaller than the polyamide branches. Preferably its molecular weight should be less than 2000, more preferably less than about 700. The polyamide branches can be polymerised by the process usually used for the preparation of polyamides from α,ω-amino acids or through hydrolytic ring-opening polymerisation of lactams, for example ε- caprolactam or laurylolactam. These processes are described for example in Kunats off-Handbuch Band VI, pp. 168-202, Carl Hansβr Vβrlag, Munich (1966). Instead of the usual chain length regulators, the multifunctional core of the invention is now added. The monomer : multifunctional core molar ratio is chosen so that the desired chain length is obtained at almost complete polymerisation. This ratio is therefore partly dependent on the number of functional groups per core molecule. In general, this molar ratio will be between lOn and 250n, n being the number of functional groups per core molecule. If ε-caprolactam is used as the monomer , the star—shaped polyamide can for example also be synthesised using the process described by Flory c.s. The process according to the invention is however preferred. In the process according to the invention for the preparation of star-shaped branched polyamides through the polymerisation of a lactant in the presence of a multifunctional core compound the polymerisation is carried out in the presence of water (0.5-30 mol.%, relative to the monomer) and optionally a catalyst, at atmospheric or elevated pressure, ,0,1-3 MPa, at a temperature between 220 and 280°C, after which the polyme isation is continued in the solid phase in a second reaction step, at reduced pressure and/or in an inert gas atmosphere, at a temperature between about 160°C and about 10°C below the melting temperature of the reaction product obtained in the first step, until a desired degree of polyme sa ion is obtained. It has most surprisingly been found that, in the case of the process according to the invention, the reaction product obtained in the first step is already very tough and strong even after a relatively short polymerisation time, its toughness and strength corresponding to those of the corresponding linear polyamide obtained after longer polymerisation - this in contrast to the brittle product that is obtained with the process according to Flory c.s. Postcondensa ion in the solid phase results in a white product with polyamide branches that may have a very high molecular weight. High' is understood to mean Mn > 5000, preferably > 7000, or even more preferably > 10,000. The temperature of the first polymerisation step is generally chosen to be between about 220 and 280°C, Preferably the reaction temperature is between about 230 and 275°, more preferably between about 240 and 270°C. The pressure in the reactor is generally atmospheric, but may optionally be set to a value between 0.1 and 3 MPa (1-30 bar). The amount of water present at the beginning of the polymerisation is not critical? usually between 0.5 and 30 mol.% water is chosen, relative to the - 7 - amount of monomer. An amount of between 5 and IS mol.% is preferred. The presence of the catalyst contributes to a short reaction time, as required to realise a desired degree of polymerisation. In principle the catalysts usually used for hydrolytic polymerisation are suitable in this case too. In the polymerisation of caprolactam in particular arainocaproic acid is preferable. The amount of catalyst to be used for the polyme sation may vary within a wide range, for example between 0,05 and 3 mol.%, relative to the monomer, preferably between 0.1 and 2 mol.%. If the acid catalyst simultaneously serves as a chain-terminating agent, the amount of catalyst to be used will be partly dependent on the desired molecular weight of the polyamide branches. From the fact that the molecular weight or the degree of polymerisation can still increase considerably in solid-phase aftercondensatiσn it can be concluded that the product obtained after the first step in the polymerisation process is a composition comprising a mixture of star-shaped branched polyamide and linear polyamide. The degree of polymerisa ion of the polyamide branches of the star-shaped branched polyamide is about the same as that of the linear polyamides in the composition if the catalyst and the functional groups of the core molecule are identical and the reaction time is sufficient. As already mentioned, this composition has mechanical properties that correspond to those of a linear polyamide with a significantly higher degree of polymerisation. For example, a polyamide composition with ductile fracture properties is obtained already after a polymerisation time after which the corresponding linear polyamide still shows brittle fracture behaviour. The invention therefore also relates to a tough polyamide composition substantially comprising a) a linear polyamide and b) a star-shaped branched polyamide. The degree of polymerisation of the polyamide branches of the star-shaped branched polyamide must be at least half of that of the linear polyamide, preferably at least about the same as that of the linear polyamide. Moie in particular the invention relates to a tough polyamide composition comprising a) a linear polyamide with a degree of polymerisation that is insufficient for obtaining ductile fracture behaviour b) a star-ahaped branched polyamide with a degree of polymerisation that is at least about the same as that of the linear polyamide. It is also possible to obtain such tough polyamide compositions by mixing a linear polyamide and a star- shaped branched polyamide in the melt. The degree of polymerisation of the star-shaped branched polyamide may then in principle be chosen independently of that of the linear polyamide. The process according to the invention is however strongly preferable. The star-shaped branched polyamide according to the invention has a high thermal stability that manifests itself in for example a white polymer. Polyamides of the kind described by Warakomski show a yellowish brown discolouration. The star-shaped branched polyamide according to the invention can easily be polymerised to a high molecular weight and will retain this high molecular weight even after long heating in the melt, without any increase in the melt viscosity - this in contrast to the star-shaped branched polyamides described by Flory c.s., which then show decomposition and crosslinking. Also the short polymerisation initiation time and the high polyme isation rate are major advantages in the preparation according to the invention. The detailed description and the experiments have been restricted to homopolyamide. However, it will be clear to a person skilled in the art that copolyamidee are also within the scope of the invention and that the term 'polyamide' hence includes both homopolyamide and copolyamide. Where mention is made of amine or carboxyl groups, those groups are understood to include groups that can yield amine and/or carboxyl groups under the polymerisation conditions, for example esters and amides. The invention will now be elucidated with reference to the following examples and comparative examples, without however being limited thereto. Example I a. Preparation of 2.4,6-trisaminocaproic acid-1.3.5- triazine (TACT) k solution of 154 g (3.8 mol,) of sodium hydroxide and 335 g (2,56 mol.) of ε-aminocaproic acid in 600 ml of water was slowly added, drop by drop, with intensive stirring, to a suspension of 78.8 g (0.428 mol) of cyanuric chloride in 650 ml of ice water. The temperature was kept between 0 and 5°C. The stirring was continued for 2 hours at 0-5 β Cι after which the temperature was raised to 50°C and maintained at that value for 4 hours, and finally the reaction mixture was kept at 100°C for 1 hour, with constant stirring. Then the reaction mixture was brought to a pfi of 4.5 with the aid of a 10% sulphuric acid solution, at 60°C. The precipitate formed was removed through filtration and rinsed with water. The melting point of the white powder was 186-8°C. Capillary electrophoresis revealed a purity of 97%. b. Polyme iaation of ε-caprolactam and the core compound TACT 100 grams of ε-caprolactam, 1 gram of ε- aminocaproic acid, 2 grams of water and different amounts of TACT (required for calculated branch lengths of 25 to 200 units) were mixed in a glass tube at 90°C. The tube was fitted with a reflux cooler and was heated to 260~270°c in a nitrogen atmosphere and then kept at this temperature for 11 hours. After cooling, the tube was broken and its contents were ground and rinsed twice with boiling water to remove unreacted caprolactam. The polymer obtained was white. Some of the mechanical properties of the rinsed polymer were measured/ the melt viscosity was determined and also he intrinsic viscosity; the melt viscosity as a so-called zero viscosity at 230", that is, the dynamic melt viscosity at 0 shearing force using a Rheometrix 800 parallel plate apparatus; the solution viscosity as a relative viscosity, h rβ ι« measured on a solution of 1 gram in 100 ml of 85% formic acid. The mechanical properties were measured using injection-moulded specimens with the indicated standard test methods, using samples that were obtained by carrying out the above polymerisation on a 500-gtams scale. The samples were dried for 24 hours at 80°C under a vacuum before the tests. The results are shown in Table 1. Example II Rinsed products obtained as described in Example lb were subjected to postcondensation at reduced pressure, under a nitrogen vent, for 4 hours at 190°C, During this postcondensation a further increase in the molecular weight of the polyamide branches was observed (Table 2). Apparently the product that was obtained after the first reaction step still contained a substantial fraction of linear polyamide besides star-shaped branched polyamide. During the postcondensation process a final condition is asymptotically reached, at which no significant amount of linear polyamide is any longer present in addition to the star-shaped branched polyamide, and at which the melt viscosity has a constant value. The melt viscosity shows Newtonian behaviour and is dependent on the shear rate to a small extent only. Only at branch lengths of 200 monomeric units does the melt viscosity start to increase at low shearing forces. TABLE 1 10 IS half of t e samp es s ows r tt e racture **> brittle fracture TABLE 2 It is noteworthy that whereas it was impossible to realise branch lengths of ftn > 5000 without crosslinking with the star-shaped branched polyamides of Flory cs., this can be realised without problems with the star-shaped branched polyamide according to the invention, using conventional polyme isation techniques. The star-shaped branched polyamide according to the invention shows a high melt stability. In 1 hour at 230°C no changes were found to occur in the melt viscosity (see Figure 1), Figure 1 shows the melt iscosity (ή*) and the phase angle (Δ) as a function of rotation velocity in the dynamic melt viscosity measurement at 5, 11, 15, 32 and 35 minutes in the melt at 230 β C. Example III Example lb was repeated, only 4-aminαmethyl- 1,8-octanediamine * (AMOD) waβ used instead of (TACT). Table 3 shows the results of the experiments. from Monsanto TABLE 3 These results are very similar to those of Table 2. Comparative experiment 1 Experiment lb was repeated, only dend nters were used as cores instead of (TACT). The dendri ers were the amine-terminated polypropylene imines of the first, second and third generation, having 4 and 8 amine terminal groups, respectively. (DAB(FFA) 4 , 1,4- diaminobutane-N,N'-tetra-l-propylamine and DAB(PPA) β . The structure and preparation of these dendrimers, which show a close similarity to Warakomski 's amine-terminated polyethylene imines, are described in for example Angew. Chem. Int. Ed. 32., 1308-1311 (1993). A brown product with inferior properties was obtained; see Table 4. 5739 15 - TABLE 4

Claims: C I M S 1. Star-shaped branched polyamide with at least 3 polyamide branches that is formed from a multifunctional core having functional groups chosen from the group of ami .e and carboxyl groups, characterised in that the amine or carboxyl groups a e bound (1) to an acyclic compound in which branching occurs, if it is branched, at a carbon atom or (2) via an acyclic chain to a heterocyclic compound. 2. Star-shaped branched polyamide according to Claim 1, characterised in that the acyclic compound is a branched alkane. 3. Star-shaped branched polyamide according to Claim 1, characterised in that the heterocyclic compound shows pointsymmetry. 4. Star-shaped branched polyamide according to Claim l, characterised in that the heterocyclic compound is a triazine. 5. Star-shaped branched polyamide according to Claim 4, characterised in that the triazine is a melamine derivative. 6. Star-shaped branched polyamide according to Claim 1, characterised in that the acyclic chain bound to the heterocyclic compound is derived from arainocaproic acid. 7. Star-shaped branched polyamide according to Claim 6, characterised in that the multifunctional nucleus is 2 , 4,6-trisaminocaproic acid-1,3,5- triazine. 8. Star-shaped branched polyamide according to Claim 2, characterised in that the multifunctional core is 4-aminometh l-l,8-octanediamine. 9. Polyamide composition substantially comprising 739 - 17 - a. a linear polyamide b, a star-shaped branched polyamide * which shows ductile fracture behaviour. 10. Polyamide composition according to Claim 9, characterised in that a. the linear polyamide is.a polyamide with a degree of polymerisation that is insufficient for it to show ductile fracture behaviour and b. the polyamide branches of the star-shaped branched polyamide have a degree of polymerisation that is at least the same as that of the linear polyamide. 11. Process for the preparation of the polyamide composition according to Claim 9 or Claim 10ft through polymerisation of a lactam in the presence of a multifunctional core compound/ in the presence of water and optionally a catalyst, at a temperature between 220 and 280°C and at atmospheric or elevated pressure. 12. Process according to Claim 11, characterised in that a. the amount of multifunctional core compound relative to the monomer is 1: (10-250).n, where n is the number of functional groups per core molecule b. the water content is between 0.5 and 30 mol.%, relative to the monomer c the pressure is between 0.1 and 3.0 MPa. 13. Process according to Claim 11 or Claim 12, characterised in that the catalyst is the α r ω- a ino acid corresponding to the lactam. 14. Process according to Claim 11, characterised in that the lactam is ε-caprolactam. 15. Process according to Claim 14, characterised in that the catalyst is aπύnocaproic acid. 16. Process according to any one of Claims 11-15, characterised in that the amount of catalyst is 0.05-3 mol.%, relative to the monomer. 17. Process for the preparation of a star-shaped melt stable branched polyamide, through postcondensation in the solid phase under a vacuum or in an inert gas atmosphere, at a temperature between about 160°C and 10°C.below the melting temperature of the product obtainable with the preparation method according to any one of Claims 11-16. 18. Process according to any one of Claims 11-17, characterised in that the functional groups of the core compound are chosen from the group of amine or carboxyl groups, the amine or carboxyl groups being bound (1) to an acyclic compound in which branching occurs, if it is branched, at a carbon atom or (2) via an acyclic chain to a heterocyclic compound showing point symmetry. 19. Product obtained by using the star-shaped branched polyamide according to any one of Claims 1-8. 20. Product obtained by using the polyamide composition according to any one of Claims 9-10. 20. Star-shaped branched polyamide, polyamide composition and process for the preparation thereof as described in the description and the examples.

Inventors: ABERSON RENE, DE BRABANDER-VAN DEN BERG ELLE, NIJENHUIS ATZA JAN, SERNE MARTIEN, ABERSON, RENE, DE BRABANDER-VAN DEN BERG, ELLEN, MARLEEN, MONIQUE, NIJENHUIS, ATZA, JAN, SERNE, MARTIEN
Applicants: ABERSON RENE, BRABANDER VAN DEN BERG ELLEN M, DSM NV, NIJENHUIS ATZA JAN, SERNE MARTIEN, ABERSON, RENE, DE BRABANDER-VAN DEN BERG, ELLEN, MARLEEN, MONIQUE, DSM N.V., NIJENHUIS, ATZA, JAN, SERNE, MARTIEN
Application year: 1996
Main classification: C08G69
IPC codes: C08G69, C08G81, C08G85