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    • 专利摘要:
    A method of manufacturing a thermoplastic material, in particular a mechanical part based on said material, characterized in that it comprises at least one injection molding step or a step implemented by extrusion, a composition of polyamide for thermoplastic material or composition of thermoplastic material, said material comprising a thermoplastic matrix based on at least one thermoplastic polymer.
    公开号:FR3019822A1
    申请号:FR1453347
    申请日:2014-04-15
    公开日:2015-10-16
    发明作者:Thierry Briffaud；Gilles Hochstetter；Mathieu Capelot
    申请人:Arkema France SA；
    IPC主号:
    专利说明:

    [0001] The invention relates to a process for the manufacture of a thermoplastic material comprising at least one injection molding step or comprising a step of extrusion molding of a thermoplastic material comprising at least one injection molding step or comprising a step of extrusion molding. a composition of or for a thermoplastic composite material with a semicrystalline polyamide (PA) matrix having a glass transition temperature Tg of at least 90 ° C and a melting temperature Tf of less than or equal to 280 ° C, in particular mechanical parts based on said material, the use of said composition for pieces of material as well as the resulting part and for applications in the fields of: automotive, railway, marine, road transport, wind power , sport, aeronautics and space, building, signage and recreation. EP 0261 020 discloses the use of reactive semicrystalline prepolymers based on PAs 6, 11 and 12 for the manufacture of a thermoplastic composite by a pultrusion process. Prepolymers of aliphatic structure as described have low Tg and insufficient mechanical performance when hot. EP 550 314 describes, among its examples, (nonreactive) copolyamide compositions in search of melting temperatures above 250 ° C and limited Tg's with most of the examples cited having too low Tg (<80 ° C). or too high Tf (> 300 ° C). EP 1 988 113 discloses a molding composition based on a 10T / 6T copolyamide with: 40 to 95 mol% of 10% - 5 to 40% of 6T. In particular, polyamides having a high melting point and greater than 270 ° C. are used. The examples mentioned and Figure 1 teach us that the melting temperature of these compositions is at least about 280 ° C. WO 2011/003973 discloses compositions comprising from 50 to 95 mol% of a linear aliphatic diamine unit having from 9 to 12 carbon atoms and terephthalic acid and from 5 to 50% by weight terephthalic acid to a mixture of 2,2,4 and 2,4,4 trimethylhexanediamine. US 2011306718 discloses a process for pultrusion of low Tg reactive aliphatic polyamides associated with chain extenders of polymeric structure bearing several (and far greater than 2) functions of anhydrides or epoxides. This document does not describe any non-polymeric extender. The drawbacks of the state of the art, with the absence of a good compromise between mechanical performance and processability (ease of processing) at lower temperature with a shorter production cycle time are surmounted by the solution of the present invention which uses semi-crystalline PA compositions, allowing easier operation at lower temperatures with a saving on the overall energy balance of the process of implementation and in particular by injection, injection molding or extruding, a shorter production cycle time and improved productivity, by rapid crystallizability of said polyamide polymer and while maintaining a high level of mechanical performance of said final materials. More particularly, in the case of the method using reactive compositions, it is desired to have faster reaction kinetics while having a higher crystallization rate and / or crystallization temperature of the polymer also formed. The choice of a semicrystalline polyamide polymer, as a matrix of the material in the process of the invention, has as interest compared to amorphous polyamides, significantly improved mechanical performance, especially when hot, such as resistance to creep or tired. In addition, having a melting point above 200 ° C. has the advantage in the automobile of being compatible with cataphoresis treatments, which is not possible with an amorphous PA structure. As for amorphous materials, a Tg greater than or equal to 90 ° C is required to ensure good mechanical properties for the material over the entire operating temperature range, for example up to 90 ° C. for wind turbines, up to 100 ° C. ° C for the automobile and up to 120 ° C for the aeronautics. On the other hand, a melting point that is too high, in particular greater than 280.degree. C., is, however, detrimental because it requires the use of the material at higher temperatures with constraints of molding material to be used (and heating system associated) and overconsumption of energy with in addition to the risks of thermal degradation by heating at temperatures higher than the melting temperature of said polyamide, with consequent assignment of the properties of the final thermoplastic matrix and the resulting material. The crystallinity of said polymer should be as high as possible but with a not too high melting temperature Tf (mp 280 ° C. and more particularly 270 ° C.) to optimize the mechanical performance and the crystallization rate and / or the crystallization temperature. highest possible, this to reduce the time of extrusion, injection or molding before ejection of the molded part with a selective choice of the composition of said semi-crystalline polyamide. Therefore, the object of the present invention is a process for manufacturing a thermoplastic material by injection, injection molding or extrusion of specific compositions of thermoplastic materials, in particular based on semicrystalline polyamide, having a good compromise between performance high mechanical strength (mechanical strength) especially hot and easy implementation. This means that the objective is to use compositions which are easy to implement with lower processing and processing temperatures than those of other compositions of the state of the art, with a balance sheet overall energy efficiency of more favorable implementation, shorter cycle time and higher productivity. More particularly, the solution of the invention, in the case of the use of reactive compositions, allows using compositions based on semi-crystalline reactive polyamide prepolymers, both reaction kinetics and kinetics of rapid crystallization with a shorter cycle time. More particularly, the polyamide polymer matrix while having a high Tg and a limited Tf as defined, with an easy implementation of said material, must also have a high crystallization rate, characterized firstly by a difference between melting temperature and of crystallization Tf-Tc not exceeding 50 ° C, preferably not exceeding 40 ° C and more particularly not exceeding 30 ° C. More preferably, this difference Tf-Tc does not exceed 30 ° C., unless Tf-Tg is <150 ° C., in which case (Tf-Tg <150 ° C.) the difference Tf-Tc can vary up to 50 ° C. vs. The mechanical performance or mechanical strength of the material can be evaluated by the variation of the mechanical module between the ambient temperature (23 ° C) and 100 ° C with a maintenance of at least 75% of the mechanical performances, in terms of module , compared to those at room temperature (23 ° C). Therefore, the object of the invention is to develop a method of manufacturing a thermoplastic material by injection, injection molding or extrusion of a polyamide composition meeting these needs. Thus, the first object of the invention relates to a method of manufacturing a thermoplastic material by injection, injection molding or extrusion of a specific semi-crystalline polyamide (PA) composition for a thermoplastic material or a thermoplastic material composition. , with a thermoplastic matrix having a Tg of at least 90 ° C and a Tf of less than or equal to 280 ° C, preferably less than 280 ° C, and more particularly of manufacturing mechanical parts based on said material. This composition may be reactive via prepolymers reactive with each other by condensation or with a chain extender by polyaddition and without elimination of volatile by-products. It may alternatively be a non-reactive composition based on polymeric polyamides corresponding to the final polymer of the thermoplastic matrix. Said specific composition is based on the selective choice of at least two different amide units A and B and specific molar proportions with optional presence of at least a third (C) and optionally a fourth (D) unit amide, these patterns being different from each other. Another object of the invention relates to the use of said specific composition of PA for the manufacture of a thermoplastic material of the same composition and more particularly of mechanical parts based on this material by injection, injection molding or extrusion. Another object of the invention relates to the thermoplastic material which results from said material composition.
    [0002] Finally, the invention covers a mechanical part made of material obtained by the specific process of the invention or which results from the use of the PA specific composition of the invention. Therefore, the first object relates to a method of manufacturing a thermoplastic material, in particular a mechanical part based on said material, characterized in that it comprises at least one injection step, injection molding or molding of a composition for a thermoplastic material or a thermoplastic material composition, said material comprising a thermoplastic matrix based on at least one thermoplastic polymer, with, with respect to said composition: said thermoplastic matrix polymer being a semicrystalline polyamide polymer with a glass transition temperature Tg of at least 90 ° C, preferably at least 100 ° C, more preferably at least 110 ° C, still more preferably 120 ° C, a melting temperature Tf less than or equal to 280 C, in particular less than 280 ° C, preferably less than or equal to 270 ° C, in particular ranging from 220 to 270 ° C, said composition comprising: ) a reactive composition comprising or consisting of at least one prepolymer (or oligomer, with oligomer and prepolymer meaning the same thing for the rest) reactive polyamide, said composition being a precursor composition of said polyamide polymer of said matrix, or alternatively to a b) a non-reactive composition of at least one polyamide polymer, said composition being that of said thermoplastic matrix with Tg and Tf as defined above, and with: said composition a) or b) comprising or consisting of of one or more polyamides, including random or sequential copolyamides which are prepolymers (or oligomers) according to a) or which are polymers according to b) and which comprise amide units A and B different and optionally amide units C and D different, selected as follows: - A: is a majority amide unit present at a molar rate ranging from 55 to 95%, preferably from 55 to 85 %, more preferably 55 to 80%, even more preferably 55 to 75%, in particular 55 to 70%, selected from xT units, where x is a C9 to C18, preferably C9, linear aliphatic diamine, C 10, C 11, C 12 and wherein T is terephthalic acid, B is an amide unit other than A, which unit B is present at a molar level ranging from 5 to 45%, preferably from 15 to 45%, more preferably from 20 to 45%, still more preferably from 25 to 45%, in particular from 30 to 45%, as a function of the Tf of the polyamide based on unit A and with the said amide unit B being chosen from among the units x '. Wherein x 'is selected from: B1) a branched aliphatic diamine bearing a single branch (branch meaning the same) methyl or ethyl, preferably methyl, in particular 2-methyl pentamethylene diamine (MPMD) or 2- methyl octamethylene diamine (MOMD) and having a different main chain length e of at least two carbon atoms with respect to the main chain length of the diamine x of said associated A unit, preferably x '(according to B1) being MPMD or o B2) m-xylylene diamine (MXD) or B3) a C4 to C18 linear aliphatic diamine when in said unit A, said diamine x is a C11 to C18 linear aliphatic diamine and x 'is a C9 to C18 diamine when in said unit A, said diamine x is a C 9 or C 10 diamine, preferably with a difference of at least two carbon atoms between the diamine chain x of said unit A and the diamine chain x 'of said unit B, and preferably said unit B is chosen from the units x'.T, where x 'is the MPMD according to option B1) or the MXD according to option B2) or a linear aliphatic diamine as defined above according to option B3) or more preferably x' is MPMD according to B1) or the MXD according to B2) and even more preferably x 'is the MXD according to B2) - C: optional amide pattern diff are of A and B and selected from amide units based on (meaning comprising) a cycloaliphatic and / or aromatic or x'T-based structure as defined above for B but with x 'different from x' for the B-D unit: optional amide unit other than A, B and C, when C is present and chosen from aliphatic amide units derived from: o amino acids or lactams C6 to C12, preferably C6, C11 and C12 or mixtures thereof, or the reaction of a linear C 6 to C 18, preferably C 6 to C 12, aliphatic diacid and a linear C 6 to C 18, preferably C 6 to C 12, aliphatic diamine or mixtures thereof, and provided that the sum of the molar levels A + B + C + D is equal to 100%, said composition being free of reinforcing fibers. The sum of the molar rates in the absence of C and D is reduced to A + B = 100%, with A and B being 100% complementary. If C is present without D, then this sum is reduced to A + B + C = 100%. If only D is present without C, said sum of 100% corresponds to A + B + D. Said composition is more particularly a composition for thermoplastic material. This means that it makes it possible to obtain a thermoplastic material by injection, injection molding or extrusion. According to a first possibility in the process of the invention, said composition of the invention, said polyamide, whether it is a polymer or a prepolymer, comprises said amide unit according to C, other than A and B, or the unit C as defined above is present and as a partial replacement of B and at a molar level of up to 25%, preferably up to 20%, more preferably up to 15% with respect to said unit B. When the unit C is present and that it corresponds to x'T with x 'as defined above for the pattern B, in this case C being different from B by definition, said pattern C can be based on x' being defined according to B1 and in this case case said pattern B may have x 'defined according to either B2 or B3. If C is based on x 'according to B2, in this case the pattern B can be based on x' being according to B1 or B3. If C is based on x 'according to B3, in this case the pattern B may be based on x' being defined according to B1 or B2.
    [0003] More particularly, in this unit C of said composition, said aromatic structure may be chosen for example from the isophthalic and / or naphthalene structure. A terephthalic structure is possible in particular for the diacid component when the diamine is cycloaliphatic. Said cycloaliphatic structure may be chosen from a cyclohexane ring-based structure or a decahydronaphthalenic ring-based structure (hydrogenated naphthalenic structure). Preferably, the structure of C is derived from an aliphatic diamine and a cycloaliphatic and / or aromatic diacid, for example as defined above, or a cycloaliphatic diacid and diamine, for example as defined above. above. More particularly, said unit C is chosen from units derived from: a cycloaliphatic diamine and terephthalic acid or diacid chosen from isophthalic, naphthenic or cyclohexane and diamine x or x 'as defined above for the patterns A and B respectively. According to another variant of the composition of the invention, said unit D is present and partially replaces B with a molar level of up to 70%, preferably up to 15% relative to said unit B. Thus, according to this variant, said composition comprises said unit D as defined above, in particular chosen from: amino acids or lactams C6 to C12, preferably C6, C11 and C12 or mixtures thereof or the units resulting from the reaction of a linear aliphatic diacid C6 to C16, preferably C6 to C12 and a linear aliphatic diamine C6 to C18, preferably C6 to C12 and preferably with the units A and B respectively being based on diamines x and x ' as defined above.
    [0004] Preferably, the C and / or D unit, when present, partially replaces the B unit with a molar ratio (C + D) of up to 70% and preferably less than 40% with respect to the molar ratio of said B unit. as defined according to the invention. Thus, a part of the unit B as defined according to the invention which represents less than 50%, preferably less than 40% by mol relative to B, can be replaced by a C and / or D unit as defined above. according to the invention. More particularly, the difference Tf-Tc, between the melting temperature Tf and the crystallization temperature Tc of said polymer (polyamide) matrix, does not exceed 50 ° C., preferably does not exceed 40 ° C. and more particularly does not exceed 30 ° C. ° C.
    [0005] In particular, Tf-Tc does not exceed 30 ° C unless Tf-Tg is less than 150 ° C, in which case Tf-Tc can be up to 50 ° C. According to a particular option, the enthalpy of crystallization of said matrix polymer, measured in Differential Scanning Calorimetry (DSC) according to Standard 150 11357-3, is greater than 40 J / g, preferably greater than 45 Jig. Preferably, said amide unit A, as defined according to the invention above and hereinafter, is present at a molar level ranging from 55 to 80%, more preferably from 55 to 75%, even more preferably from 55 to 70%. %, with respect to all the units of said matrix polymer (polyamide) as defined above according to the invention.
    [0006] According to a first preferred option in the process according to the invention described above, said composition has a unit B with x 'defined according to the option 131 described above, in particular with as diamine more preferred for said pattern B, being MPMD. The unit A remains as defined above, that is to say xT, with x a linear aliphatic diamine of C8 to C18, preferably C8, C10, C11 or C12- According to a second preferred option in the process according to US Pat. invention, said composition has a pattern B where x is the MXD according to option 62 defined above. Pattern A remains as defined for the first option cited. This second option constitutes together with the first mentioned above the most preferred of the invention and in particular this second option is the most preferred of the invention.
    [0007] A third preferred option is that where B is defined according to the option BI or B2 or 63 as defined above and with the presence of a pattern C as defined above replacing B and up to 25%, preferably up to 20%, more preferably up to 15% by mole and in particular with B being defined according to the first or second option as defined above.
    [0008] More preferably still, said polyamide composition is based on the A and B patterns selected as follows: for the pattern A being 9T, said pattern B is selected from: 10T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of with B being from 30 to 45%, for the pattern A being 10T, said pattern B is selected from: 9T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 25 to 45%, for pattern A being 11T, said pattern B is selected from: 9T, 10T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 9T, 13T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 45% for pattern A being 12T, said pattern B is selected from: 9T, 10T, 11T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 9T, 10T, 14T, 15T , 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 45%. According to this selection, in the method according to the invention a first more particular composition can be defined, with the pattern A being a 9T pattern and the pattern B being selected from: 10T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar rate of B ranging from 30 to 45%. A second particular composition corresponds to a pattern A being a 10T pattern and the pattern B being selected from: 9T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 12T , 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 25 to 45%. A third particular composition corresponds to a pattern A being a pattern 11T and the pattern B being selected from: 9T, 10T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 9T, 13T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 45%. Finally, another particular composition corresponds to a pattern A being a pattern 12T and the pattern B being selected from: 9T, 10T, 11T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 9T, 10T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 45%. With regard to the reactivity or otherwise of said polyamide composition, according to a first option, said polyamide composition may be a non-reactive composition according to b). This means that said composition is the same as that of the polymer (polyamide) matrix of said material because there is no reaction in this composition, which remains stable and non-evolutive in terms of molecular weight during its heating for the implementation of the material of the invention. The characteristics of the polyamide polymer in this composition are the same, with Tg and Tf as defined above, than those of the final polymer which is the semi-crystalline polyamide obtained by a reactive composition a) (see below), said polymer constituting by definition said thermoplastic matrix of said material. The polyamides according to b) are obtained by conventional polycondensation reaction from the monomeric components which are diamines, diacids and optionally amino acids or lactams, with the proportion and nature of the monomers being chosen according to the selected units of the invention, and B and optionally C and D. The number-average molecular weight Mn of said final polymer (polyamide) of the thermoplastic matrix of said material is preferably in a range from 10,000 to 40,000, preferably from 12,000 to 30,000. correspond to inherent viscosities greater than or equal to 0.8. These polyamides according to composition b) are non-reactive, either by the low level of reactive (residual) functions present, in particular with a level of said functions <120 meq / kg, or by the presence of the same type of terminal functions at the end of the reaction. chain and therefore not reactive with each other, either by modifying and blocking said reactive functions by a monofunctional reactive component, for example for the amine functions by modification reaction with a monoacid or a monoisocyanate and for carboxyl functions by reaction with a monoamine. When said final matrix polymer is derived from a reactive prepolymer in a reactive precursor composition a), this reactive prepolymer has an Mn of at least two times lower than that of said final matrix polymer.
    [0009] According to a second option, said polyamide composition may be a reactive prepolymer composition according to a) and precursor or precursor composition of said polyamide polymer of said matrix of the material. In this second option, according to the reactive composition a), three more particular possibilities can be distinguished. According to a first possibility, said composition a) may comprise or consist of at least one reactive (polyamide) prepolymer carrying on the same chain (ie on the same prepolymer), two terminal functions X 'and Y 'functions respectively coreactive between them by condensation, with X' and Y 'being amine and carboxy or carboxy and amine respectively. According to a second possibility, said reactive composition a) may comprise or consist of at least two polyamide prepolymers which are reactive with one another and each carrying two identical terminal functions X 'or Y' (same for the same prepolymer and different between the two). prepolymers), said function X 'of a prepolymer being able to react only with said function Y' of the other prepolymer, in particular by condensation, more particularly with X 'and Y' being amine and carboxy or carboxy and amine respectively. This condensation reaction (or polycondensation) can cause the elimination of by-products. These can be removed by preferably working in a method using open mold technology. In the case of a closed mold process, a step of degassing, preferably under vacuum, by-products removed by the reaction is present, in order to avoid the formation of microbubbles by-products in the final material, which (microbubbles) can affect the mechanical performance of said material if they are not removed as well. According to a third option of reactive composition a), said composition a) or precursor composition a) may comprise or consist of: a1) at least one prepolymer of said thermoplastic polyamide polymer (matrix) as already defined above with this prepolymer carrier of n terminal reactive functions X, identical chosen from: -NH2 (amine), -CO2H (carboxy) and -OH (hydroxyl), preferably -NH2 (amine) and -CO2H (carboxy), with n being 1 to 3 preferably 1 to 2, more preferably 1 or 2, more particularly 2 a2) at least one Y-A'-Y chain extender, with A 'being a hydrocarbon biradical of non-polymeric structure (neither polymer nor oligomer nor prepolymer ), carrying 2 identical Y terminal reactive reactive functions by polyaddition (without elimination of reaction by-product), with at least one function X of said prepolymer a1), preferably with a molecular mass of less than 500 and more preferred less than 400. NH2 (amine) means primary and secondary amine. In the latter case (third option), the semi-crystalline structure of said polyamide polymer of the matrix of said material is essentially provided by the structure of said prepolymer a1) which is also semi-crystalline. As suitable examples of lengtheners a2) as a function of the X functions carried by said semi-crystalline polyamide prepolymer al), the following may be mentioned: when X is NH 2 or OH, preferably NI-12 o is the Y-chain extender A'-Y is chosen from among the groups: maleimide, optionally blocked isocyanate, oxazinone and oxazolinone, cyclic anhydride, preferably oxazinone and oxazolinone and A 'is a carbon spacer or carbon radical carrying the functions or reactive groups Y, selected from: - a covalent bond between two functions (groups) Y in the case where Y = oxazinone and oxazolinone or - an aliphatic hydrocarbon chain or an aromatic hydrocarbon and / or cycloaliphatic chain, the latter two comprising at least one ring of 5 or 6 optionally substituted carbon atoms, optionally with said aliphatic hydrocarbon chain optionally having a molecular weight of 14 to 200 g.mor1 bones where the chain extender Y-A'-Y is Y being a caprolactam group and A 'may be a carbonyl radical such as carbonyl biscaprolactam or A' may be terephthaloyl or isophthaloyl, o is said Y-A'-Y chain carries a group Y of cyclic anhydride and preferably this elongator is chosen from a cycloaliphatic and / or aromatic carboxylic dianhydride and more preferably it is chosen from: ethylenetetracarboxylic dianhydride, pyromellitic dianhydride, dianhydride 3 , 3 ', 4,4'-biphenyltetracarboxylic, 1,4,5,8-naphthalenetetracarboxylic dianhydride, perylenetetracarboxylic dianhydride, 3,3', 4,4'-benzophenone tetracarboxylic dianhydride, 1,2,3 dianhydride, 4-cyclobutanetetracarboxylic acid, hexafluoroisopropylidene bisphthalic dianhydride, 9,9-bis (trifluoromethyl) xanthenetetracarboxylic dianhydride, 3,3 ', 4,4'-diphenylsulfonetetracarboxylic dianhydride, bicyclo [2.2.2] oct-7-ene-2,3,5,6-tetracarboxylic dianhydride, 1,2,3,4-cyclopentanetetracarboxylic dianhydride, 3,3 'dianhydride, 4,4'-diphenyl ether tetracarboxylic acid or mixtures thereof and when X is COOH: said Y-A'-Y chain extender corresponds to: Y Y chosen from the groups: oxazoline, oxazine, imidazoline, aziridine, such as 1, 1'-iso- or tere - phthaloyl-bis (2-methyl aziridine), or epoxy ^ A 'being a carbon spacer (radical) as defined above. More particularly, when in said Y-A'-Y extender, said Y function is selected from oxazinone, oxazolinone, oxazine, oxazoline or imidazoline, in this case, in the chain extender represented by Y-A'-Y, A can represent an alkylene such that - (CH2) m - with m ranging from 1 to 14 and preferably from 2 to 10 or A 'can represent a cycloalkylene and / or a substituted arylene (alkyl) or an unsubstituted arylene, such as arylenes benzenes, such as o-, m-, -p phenylenes or naphthalenic arylenes and preferably A 'is arylene and / or cycloalkylene.
    [0010] In the case where Y is an epoxy, the chain extender may be chosen from: bisphenol A diglycidyl ether (DGEBA), and its hydrogenated derivative (cycloaliphatic) bisphenol F diglycidyl ether, tetrabromo bisphenol A diglycidyl ether, or hydroquinone diglycidyl ether, ethylene glycol diglycidyl ether, propylene glycol diglycidyl ether, butylene glycol diglycidyl ether, neopentyl glycol diglycidyl ether, 1,4-butanediol diglycidyl ether, 1,6-hexanediol diglycidyl ether, cyclohexanedimethanol diglycidyl ether, polyethylene glycol diglycidyl ether Mn 500, polypropylene glycol diglycidyl ether of Mn <500, polytetramethylene glycol diglycidyl ether of Mn <500, resorcinol diglycidyl ether, neopentyl glycol diglycidyl ether, bisphenol A polyethylene glycol diglycidyl ether of Mn <500, bisphenol A polypropylene glycol diglycidyl ether of Mn <500, diglycidyl esters of a carboxylic acid such as glycidyl ester of terephthalic acid or epoxidized diolefins (dienes) or epoxidized ethylenically unsaturated double fatty acids, diglycidyl 1,2-cyclohexanedicarboxylate, and mixtures thereof. Advantageously, X is NH 2 or OH, in particular NH 2 and Y is chosen from an oxazinone and an oxazolinone.
    [0011] Advantageously, X is CO2H and Y is chosen from an epoxy and an oxazoline. More preferably, X is CO2H and Y-A'-Y is selected from phenylenes bis oxazolines, preferably 1,3-phenylenebis (2-oxazoline) or 1,4-phenylenebis (2-oxazoline) (PBO ).
    [0012] In the case of carbonyl- or terephthaloyl- or isophthaloyl-biscaprolactam as Y-A'-Y chain extender, the preferred conditions avoid the elimination of by-products, such as caprolactam during said polymerization and carried out at the same time. melted state. In the eventual case cited above where Y represents a blocked isocyanate function, this blocking can be obtained by blocking agents of the isocyanate function, such as epsilon-caprolactam, methyl ethyl ketoxime, dimethyl pyrazole, diethyl malonate. Similarly, in the case where the extender is a dianhydride reacting with a prepolymer P (X) n where X = NH 2, the preferred conditions avoid any formation of imide ring during the polymerization and during implementation in the state molten.
    [0013] For X = OH or NH2, the group Y is preferably chosen from: isocyanate (not blocked), oxazinone and oxazolinone, more preferably oxazinone and oxazolinone, with the spacer (radical) A 'being as defined above. As examples of chain extenders carrying oxazoline or oxazine reactive functional groups Y that are suitable for carrying out the invention, reference may be made to those described under references "A", "B", "C" and "D". on page 7 of application EP 0 581 642, as well as to their preparation processes and the other reaction modes which are exposed to them. "A" in this document is bisoxazoline, "B" bisoxazine, "C" 1,3 phenylene bisoxazoline and "D" 1,4-phenylene bisoxazoline.
    [0014] As examples of Y-imidazoline functional chain extenders suitable for the implementation of the invention, reference may be made to those described ("A" to "F") on pages 7 to 8 and Table 1 of the present invention. page 10 in the application EP 0 739 924 as well as their processes of preparation and their modes of reaction which are exposed to it.
    [0015] As examples of Y = oxazinone or oxazolinone reactive functional chain extenders which are suitable for the implementation of the invention, reference may be made to those described under references "A" to "D" on page 7 to 8 of EP 0 581 641, and to their preparation processes and their reaction modes which are exposed to them.
    [0016] Examples of groups Y oxazinones (6-atom ring) and oxazolinones (5-atom ring) are suitable Y groups derived from: benzoxazinone oxazinone or oxazolinone, with as spacer A 'can be a single bond covalently with respective corresponding lengtheners being: bis- (benzoxazinone), bisoxazinone and bisoxazolinone.
    [0017] A 'can also be a C1 to C14 alkylene, preferably a C2 to C10 alkylene, but preferably A' is an arylene and more particularly it may be a phenylene (substituted with Y in the 1,2 or 1,3 or 1, 4) or a naphthalene radical (disubstituted by Y) or phthaloyl (iso- or terephthaloyl) or A 'may be a cycloalkylene. For the Y functions such as oxazine (6-ring), oxazoline (5-ring) and imidazoline (5-ring), the radical A 'can be as described above with A' being a simple covalent bond and with the extenders respective corresponding ones being: bisoxazine, bisoxazoline and bisimidazoline. A 'may also be a C1 to C14 alkylene, preferably a C2 to C10 alkylene. The radical A 'is preferably an arylene and, more particularly, it may be a phenylene (substituted with Y in the 1,2 or 1,3 or 1,4 positions) or a naphthalene (disubstituted with Y) or phthaloyl radical ( iso- or terephthaloyl) or A 'may be cycloalkylene. In the case where Y = aziridine (nitrogen heterocycle with 3 atoms equivalent to ethylene oxide, replacing the ether -O- with -NH-), the radical A 'may be a phthaloyl (1,1'iso- or terephthaloyl) with 1, 1 'isophthaloyl-bis (2-methyl aziridine) as an example of such an extender. The presence of a catalyst for the reaction between said P (X) n prepolymer and said Y-A'-Y extender at a level ranging from 0.001 to 2%, preferably from 0.01 to 0.5% relative to The total weight of two co-reactants mentioned can accelerate the (poly) addition reaction and thus shorten the production cycle. Such a catalyst may be chosen from: 4,4'-dimethylaminopyridine, p-toluenesulphonic acid, phosphoric acid, NaOH and optionally those described for polycondensation or transesterification as described in EP 0 425 341, page 9, lines 1 to According to a more particular case of the choice of said extender, A 'may represent an alkylene, such that - (CH 2) co- with m ranging from 1 to 14 and preferably from 2 to 10 or represents a substituted arylene alkyl or unsubstituted such as benzene arylenes (such as o-, m-, -p) or naphthalenic phenylenes (with arylenes: naphthalenylenes). Preferably, A 'represents an arylene which can be benzene or naphthenic substituted or not.
    [0018] As already stated, said chain extender (a2) has a non-polymeric structure and preferably a molecular weight of less than 500, more preferably less than 400. Said reactive prepolymers of said reactive composition a), according to the three options mentioned above, have a number average molecular weight Mn ranging from 500 to 10,000, preferably from 1000 to 6000 determined in particular by calculation from the terminal function level determined by solution potentiometric titration and the functionality of said prepolymers. Mn masses can also be determined by size exclusion chromatography or by NMR. The ratio of said lengthening agent in said polyamide polymer ranges from 1 to 20%, in particular from 5 to 20%. In the process of the invention and in the case of the reactive compositions according to definition a), said reactive prepolymers are prepared by conventional polycondensation reaction between the corresponding diamine and diacid components and optionally (depending on the D-unit) amino acids or lactams while respecting the nature and proportions of the units A and B and optionally C and D. The prepolymers bearing X 'and Y' amine and carboxy functions on the same chain can be obtained for example by adding a combination of monomers (amino acid, diamine, diacid) having an equal amount of amine and carboxy units in total.
    [0019] Another way of obtaining these prepolymers carrying a function X 'and a Y' is, for example, by combining a prepolymer carrying 2 identical functions X '= amine, with a diacid prepolymer carrier of Y': carboxy, with an overall molar ratio in acid functions equal to that of the amine functions X 'starting. To obtain prepolymers functionalized with identical functions (amines or carboxy) on the same chain, it suffices to have an excess of diamine (or amine functions overall) to have amine terminal functions or excess of diacid (or carboxy functions globally) to have carboxyl terminal functions. In the case of a prepolymer P (X) n with n identical functions X, the functionality 1 can be obtained in the presence of a monofunctional blocking component (monoacid or monoamine depending on the nature of X = amine or carboxy). Functionality n = 2 can be obtained from difunctional components: diamines and diacids with an excess of one to fix X as a function of this excess. For n = 3, for example, for a P (X) n prepolymer, the presence of a trifunctional component is required, for example the presence of a triamine (one mole per prepolymer chain) with a diamine in the reaction with a diacid . The preferred functionality for P (X) n is n = 2.
    [0020] The term "reinforcing fibers" refers to an assembly of fibers, short or long, for example mineral fibers, polymeric fibers or a mixture thereof and the composition used in the process of the invention is therefore devoid of it.
    [0021] More particularly, the method of the invention is a method of injection, injection molding or extrusion of a composition as defined above. Said composition may comprise fillers and additives other than reinforcing fibers. Suitable fillers include, for example: inorganic or organic fillers: carbon black, carbon nanotubes (CNTs), carbon nanofibrils, glass beads, recycled polymers milled in powder form.
    [0022] Among the suitable additives, mention may be made of: additives absorbing in the UV or IR so as to allow the welding of the material obtained, by a laser (UV or IR) technology and thermal stabilizers chosen from sterically hindered phenol type antioxidants or sterically hindered amines (HALS). The function of these stabilizers is to prevent thermal oxidation and the consequent photoxidation and degradation of the matrix polyamide of the material obtained. Advantageously, the process of the invention by injection, injection molding or extrusion, of a composition as defined above comprises at least one polymerization step of at least one reactive composition a) as defined above according to the invention or a molding step or implementation of at least one non-reactive composition b) as defined above according to the invention. More particularly, said process may comprise the following steps: i) injection of a composition free of fibrous reinforcement as defined above according to the invention in an open or closed mold or out of mold, ii) polymerization reaction by heating of said composition of step i), in the case of a reactive composition a) of polyamide as defined according to the invention, with chain extension (increase in molecular weight), as the case may be, by polycondensation reaction (including self-condensation of the same prepolymer), or by melt mass polyaddition reaction, with in the case of polycondensation, vacuum removal of the condensation products when it is a closed mold, with using a vacuum extraction system, otherwise and preferably with the polycondensation being carried out in open mold or out of mold, iii) implementation or molding of said composition of step i), in the the case of a non-reactive polyamide composition b) as defined according to the invention, for forming the final part in a mold or with another processing system and in the case of a reactive composition a) a step of setting by molding or by another implementation system and simultaneously with the polymerization step ii).
    [0023] Advantageously, the process of the invention according to the invention may also comprise the following steps: i) polymerization reaction in the case of a reactive composition a) of polyamide as defined above, by heating said composition of step i) with chain extension, as the case may be, by polycondensation reaction or polyaddition reaction, in bulk in the molten state, with in the case of polycondensation, a vacuum removal of the condensation products at the using a vacuum extraction system to obtain a non-reactive composition, ii) extrusion of the non-reactive composition from step i) or a non-reactive composition as defined above without fibrous reinforcement, In said process according to the invention, said implementation can be carried out preferably according to a RIM, injection-compression process, in particular in the case of a reactive composition a). Another subject of the invention relates to the use of a composition as defined above or the use of a non-reactive semi-crystalline polyamide polymer as defined according to said composition b) or a polymer that can be obtained from a reactive composition as defined according to said composition a) for the manufacture of a thermoplastic material, more particularly of a mechanical part, such as single-layer or multilayer pipe, or film based on said composition or said material. According to a more particular use, said mechanical parts of said material relate to applications in the field of automotive, electrical or electronic, railway, marine, wind, photovoltaic, solar, including solar panels and components solar power plants, sports, aeronautics and space, road transport (for trucks), building, civil engineering, billboards or recreation.
    [0024] Advantageously, said parts for applications in the automobile are parts under the bonnet for the transport of fluid, in particular in air intake devices, cooling (for example by air, coolant, ...) , transportation or transfer of fuels or fluids (such as oil, water, ...).
    [0025] Advantageously, said mechanical parts for electrical or electronic applications are goods of electrical and electronic equipment, such as encapsulated solenoids, pumps, telephones, computers, printers, fax machines, modems, monitors, remote controls, cameras, circuit breakers, sheaths of electrical cables, optical fibers, switches, multimedia systems. These items of electrical and electronic equipment goods cover not only the structural parts of such goods (boxes, shells ...) but also their possible associated accessories (earphones, connectors, cables ...). More particularly, three more preferred applications can be distinguished as a function of the temperature of use of said pieces of material according to the invention: in the wind turbine, with a Tg of said thermoplastic matrix polyamide of at least 90 ° C - in the automobile, with a Tg of said polyamide of at least 100 ° C - in aeronautics, with a Tg of said polyamide of at least 120 ° C.
    [0026] This means that for a Tg of at least 100 ° C, it can have two possible applications: automobile and wind and if the Tg is at least 120 ° C in addition to aeronautics as an application, it can also be used wind and the automobile. The present invention also covers a thermoplastic material resulting from the use of at least one composition for thermoplastic material free of reinforcing fibers as defined above according to the present invention. Finally, the invention relates to a mechanical piece of thermoplastic material, which results from the use of at least one composition of the invention as defined above or from the use of a semicrystalline non-reactive polyamide polymer such as defined according to said composition b) or a polymer obtainable from a reactive composition as defined according to said composition a) or a thermoplastic material as defined above or which part is obtained by a method such as as defined above according to the invention. According to another option, it is a piece for a wind turbine, in particular with a Tg of at least 100 ° C.
    [0027] According to a third particular option, it is a part for aeronautics, in particular with a Tg of at least 120 ° C. According to a fourth option, it is a mechanical part for applications in the automobile such as parts under the bonnet for the transport of fluid, in particular in air intake and cooling devices (for example by air, liquid cooling, ...), transport or transfer of fuels or fluids (such as oil, water, ...). According to a fifth option, it is a mechanical part for applications in electrical or electronic such as electrical and electronic equipment, such as encapsulated solenoids, pumps, telephones, computers, printers, fax machines, modems, monitors , remote controls, cameras, circuit breakers, electrical cable ducts, optical fibers, switches, multimedia systems. Methods for determining the characteristics mentioned The melt viscosity of the prepolymer or precursor composition is measured according to the reference manual of the manufacturer of the measuring apparatus used, which is a Physica MCR301 rheometer, under nitrogen flushing. the temperature given under shear of 100 s', between two parallel planes with a diameter of 50 mm. The Mn of the prepolymer or of the thermoplastic polymer is determined from the titration (assay) of the terminal functions according to a potentiometric method (direct assay for NH 2 or carboxy) and from the theoretical functionality which is 2 (in terminal functions). for prepolymers and linear polymers prepared from bifunctional monomers alone. Measurement of intrinsic or inherent viscosity is performed in m-cresol. The method is well known to those skilled in the art. The ISO 937 standard is followed but the solvent is changed (use of m-cresol instead of sulfuric acid and the temperature is 20 ° C). - The glass transition temperature Tg of the thermoplastic polymers used is measured using a differential scanning calorimeter (DSC), after a second heating passage, according to ISO 11357-2. The heating and cooling rate is 20 ° C / min. The melting temperature Tf and the crystallization temperature Tc are measured by DSC, after a first heating, according to the ISO 11357-3 standard. The heating and cooling rate is 20 ° C / min. The enthalpy of crystallization of said matrix polymer is measured in Differential Scanning Calorimetry (DSC) according to the ISO 11357-3 standard.
    [0028] EXAMPLES A Preparation of a Polyamide Polymer Directly (Without Chain Expansion of a Reactive Prepolymer) In a 14 liter autoclave reactor, 5 kg of the following raw materials are introduced: 500 g of water, the diamine (s) - the amino acid (optionally), - the diacid (s), - the monofunctional chain regulator: benzoic acid in an amount adapted to the target Mn and variant (benzoic acid) of 50 to 100 g, - 35 g of hypophosphite of sodium in solution, - 0.1 g of WACKER AK1000 antifoam (company Wacker Silicones). The nature and molar ratios of the units and molecular structures of the polyamides (by reference test) are given in Table 1 below. The closed reactor is purged of its residual oxygen and then heated to a temperature of 230 ° C. with respect to the material introduced. After stirring for 30 minutes under these conditions, the pressurized steam which has formed in the reactor is gradually relieved in 60 minutes, while progressively increasing the material temperature so that it is established at Tf + 10. ° C at atmospheric pressure. The polymerization is then continued under a nitrogen sweep of 20 l / h until the target mass Mn indicated in the table of characteristics is obtained. The polymer is then drained by the bottom valve and then cooled in a water tank and then granulated. The results are shown in the following Table 1. Table 1: Characteristics of polymers prepared directly without reactive prepolymer Ref Type test Structure Tf (° C) / Tf - Tg (° C) Tc Tf-Tc (° C) AHc Inherent viscosity Index ends Molecular Mn / Tg index (° C) (° C) (J / g) (m-amino acid chains g / cresol composition) non meq / kg meq / kg mole reactive meq / kg (**) (calc) 1 Comparative, 10.T /6.T (59/41) 281/122 159 236 45 44 1.12 103 45 60 9600 (EP1988 113) 2 Comparative, 10.T / 6.T / 11 269/111 158 220 49 39 1.25 91 Comparative, 10.T / TMD.T 263/133 130 197 66 35 1.15 97 63 35 10250 (WO (59/41) 2011/00393) 4 Comparative 10.T (100) 314/120 194 279 35 63 insoluble 154 54 22 8700 5 Comparative 10.T / 11 (67/33) 269/84 185 232 37 50 1.19 119 55 40 9350 6 Comparative 10.T / 11 (59/41) 261/78 183 213 48 39 1.15 112 22 34 11900 7 Comparative 10.T / 10.1 (67/33) 269/110 159 205 64 32 1.12 97 48 51 10100 8 Comparative MXD. T / 11 211/111 100 (*)> 12 1.25 (59/41) 100 9 Comparative MPMD.T / 11 - / 84 - (*) - - 1,14 (59/41) 5 (*): No crystallisation on cooling (**): Milliequivalents per kilogram 23 Ref Type test Structure Tf (° C) / Tf - Tg ( ° C) Tc Tf-Tc (° C) to Hc Inherent viscosity Index ends Molecular Mn / Tg (° C) index (° C) (J / g) (m-amino acid chains g / Cresol composition) non meq / kg meq / kg molar reactive meq / kg (**) (calc) 10 According to the invention 10.T / MXD.T 270/130 140 244 26 47 1.03 143 85 42 7400 (67/33) 11 According to the invention invention 10.T / MXD.T 269/131 138 241 28 44 1.01 100 134 38 7350 (59/41) 12 Comparative, 10.T / MXD.T 262/137 125 211 51 17 0.99 136 97 37 7400 outside the invention (50/50) 13 According to the invention 10.T / MPMD.T 270/124 146 230 40 45 1.05 139 63 42 8200 (67/33) 14 According to the invention 10.T / MPMD T 264/126 138 219 45 40 1.11 155 59 27 8300 (59/41) 15 Comparative, 10.T / MPMD.T 245/127 118 185 60 22 1.12 outside the invention (50/50) 16 Comparative , 10.T / 12.T (59/41) 280/114 166 260 20 62 0.81 0 263 <10 7600 outside the invention 17 According to the invention 10 .T / 12.T / 11 271/105 166 246 25 56 0.98 169 49 32 8000 (60/24/16) 18 According to the invention 18.T / MXD.T 264/95 169 242 22 47 0, 86 174 73 35 7100 (71/29) (*): No crystallization on cooling (**): Milliequivalents per kilogram The representative tests of the invention show superior performances compared to the comparative tests outside the invention, some of which are representative of the state of the prior art cited, in particular in terms of low Tf-Tc difference (<30 ° C) and for Tf5 Tc ranging from 30 to 50 ° C with Tf-Tg difference <150 ° C. B - Preparation of a polyamide polymer by chain extension of a reactive prepolymer (or oligomer) B-1 Preparation of the reactive prepolymer P (X) n 5 kg of the following raw materials are introduced into a 14-liter autoclave reactor 500 g of water, the diamine (s), the amino acid (optionally), the terephthalic diacid, 35 g of sodium hypophosphite in solution, 0.1 g of an antifoam WACKER AK1000 (company Wacker Silicones). The nature and molar ratios of the units and molecular structures of the reactive prepolymer polyamides (by reference test) are given in Table 2 below. The closed reactor is purged of its residual oxygen and then heated to a temperature of 230 ° C of the material. After stirring for 30 minutes under these conditions, the pressurized steam that has formed in the reactor is progressively expanded in 60 minutes, while gradually raising the material temperature to Tf +. 10 ° C at atmospheric pressure. The oligomer (prepolymer) is then drained by the bottom valve and then cooled in a water tank and ground. The characteristics are presented in Table 2 below. Table 2: Characteristics of prepared prepolymers Ref Structure Tf Tg Tf-Tc Tf-Tc AH Viscosity Index Index Molecular Mn and (° C) (° C) Tg (° C) (° C) (J / g) inherent to amine acid g / mole composition (° C) (in meq / kg (*) meq / kg molar cresol) 19 According to 10.T / MXD.T 264 117 147 232 32 42 0.32 878 0 2280 l According to the invention (59/41) according to the invention (59/41) (*): Milliequivalents per kilogram B-2 Preparation of the polyamide polymer by chain extension with a type Y-YY type 10 g of the above dried and ground oligomer are mixed with a stoichiometric amount of 1,3 phenylene bis-oxazoline (PBO). The mixture is introduced under a nitrogen sweep in a DSM brand micro-extruder (volume 15 mL) with corotative conical screws preheated to 280 ° C. under rotation of the screws at 100 rpm. The mixture is left under recirculation in the micro-extruder and the increase in viscosity is monitored by measuring the normal force. After about 2 minutes, a plateau is reached and the contents of the micro-extruder are drained in the form of a rod. The air-cooled product is granulated. The results of the product analyzes are presented in Table 3 below.
    [0029] Table 3: Analytical characteristics of polyamides obtained with chain extension Ref Structure Tf Tg Tf-Tg Tc Tf-Tc AH Molecular viscosity / (° C) (° C) (° C) (° C) (° C) (J / g) inherent Composition (in molar m-cresol) According to 10.T / MXD.T 256 135 121 219 37 30 1.3 the invention (59/41) 22 According to 10.T / MPMD.T 262 128 134 210 52 36 0.82 the invention (59/41) C - Formulation of the material free of reinforcing fibers C-1 Preparation of the formulation The granules from step A are compounded on a twin-screw extruder Evolum 32 according to a profile flat temperature of 280 ° C. The flow rate is 40 kg / h and the speed is 300 rpm. The polymer (97.3% by weight) and the additives (0.3% Calcium Sterarate and 0.4% Irganox 1010) are introduced into the main hopper. The rushes are cooled in water and granulated. The 10.T / MXDT composition still exhibits a higher crystallization ability associated with a very high Tg and particularly low Tf-Tg.
    [0030] C-2 Mechanical properties (heat resistance) with temperature The granules of the formulations below are formed into 80 * 10 * 4 mm bars by injection molding using a Krauss Maffei 60 tonnes B2 equipped machine. a screw of diameter 0 30 mm. The samples were injected at 260 ° C. in a mold at 90 ° C. at 130 rpm (measured material pressure of 833 bars). The material was kept under pressure at 611 bar for 15 seconds before the mold was cooled in 20 seconds. 3-point bending tests according to ISO 178 are carried out at different temperatures on a Zwick 1 dynamometer. The spokes of the punch and the supports are 5 mm. The speed is 2 mm / min and the modulus is calculated between 0.05 and 0.25% deformation.
    权利要求:
    Claims (29)
    [0001]
    REVENDICATIONS1. A method of manufacturing a thermoplastic material, in particular a mechanical part based on said material, characterized in that it comprises at least one injection molding step or a step carried out by extrusion, a composition of polyamide for thermoplastic material or composition of thermoplastic material, said material comprising a thermoplastic matrix based on at least one thermoplastic polymer, said composition being characterized: in that said thermoplastic matrix polymer is a semi-crystalline polyamide polymer with a temperature glass transition Tg of at least 90 ° C and with a melting temperature Tf of less than or equal to 280 ° C, in that said composition comprises: a) a reactive composition comprising or consisting of at least one polyamide prepolymer reagent, said composition being a precursor composition of said polyamide polymer of said matrix, or alternatively to a), b) a non-reactive composition of at least one polyamide polymer, including the polymer derived from a), said composition being that of said thermoplastic matrix with Tg and Tf being as defined above, and - in said composition a) or b) comprises or consists of, one or more polyamides which are prepolymers according to a) or which are polymers according to b), which comprise amide units A and B different and optionally amide units C and D, selected as follows: A: is a majority amide unit present at a molar level ranging from 55 to 95%, preferably from 55 to 85%, more preferably from 55 to 80%, selected from xT units, where x is a linear aliphatic diamine of C9 to C18, preferably C9, C10, C11 and C12 and where T is terephthalic acid, - B: is an amide unit other than A, which unit B is present at a rate of molar ranging from 5 to 45%, preferably from 15 to 45%, more preferred approximately 20 to 45%, depending on the Tf of the polyamide based on unit A and said amide unit B is chosen from the units x'.T where x 'is chosen from: o B1) a branched aliphatic diamine carrying a single branching (or branching) methyl or ethyl and having a main chain length different from at least two carbon atoms from the main chain length of the diamine x of said associated A-unit, preferably x 'being the
    [0002]
    2-methyl pentamethylene diamine (MPMD) or o B2) m-xylylene diamine (MXD) or o B3) a linear aliphatic diamine in C4 to 018 when in the unit A, said diamine x is a linear aliphatic diamine in Cil at 018 and x 'is a C8 to O18 diamine when in the unit A said diamine x is a C8 or O10 diamine, and preferably B being selected from x'.T, where x' is MPMD according to B1) or MXD according to B2) or a linear aliphatic diamine as defined above according to B3) and more preferably x 'is MPMD according to B1) or MXD according to B2) and even more preferably MXD according to B2), C: optional amide unit other than A and of B, chosen from amide units based on a cycloaliphatic and / or aromatic structure or based on x'T as defined above for B but with x 'other than x' for the unit B, D: optional amide other than A, B and C when C is present and selected from aliphatic amide units from: or C 6 to C 12, preferably C 6, C 11 and O 12 lactams or mixtures thereof - the reaction of a linear C 6 to C 18 aliphatic diacid, preferably C 6 to O 12 and a linear C 6 to C 18 aliphatic diamine, of preferably C6 to 012 or mixtures thereof and provided that the sum of the molar levels of A + B + C + D is equal to 100%, said composition being free of reinforcing fibers. 2. Method according to claim 1, characterized in that said amide unit C is present and partially replaces B at a molar level of up to 25% relative to said pattern B.
    [0003]
    3. Method according to one of claims 1 to 2, characterized in that said pattern D is present and partially replacing B at a molar rate of up to 70%, relative to said pattern B.
    [0004]
    4. Method according to one of claims 1 to 3, characterized in that the difference Tf-Tc, between the melting temperature Tf and the crystallization temperature Tc of said matrix polymer, does not exceed 50 ° C, preferably does not exceed not 40 ° C, more preferably does not exceed 30 ° C.
    [0005]
    5. Method according to one of claims 1 to 4, characterized in that the crystallization enthalpy, measured in Differential Scanning Calorimetry (DSC) according to ISO 11357-3, is greater than 40 J / g, preferably greater than 45 J / g.
    [0006]
    6. Method according to one of claims 1 to 5, characterized in that said amide unit A is present with a molar level ranging from 55 to 80%, preferably from 55 to 75%, more preferably from 55 to 70% relative to to all the units of said polymer.
    [0007]
    7. Method according to one of claims 1 to 6, characterized in that said pattern B corresponds to x'T with x 'chosen according to option B1), in particular with x' being MPMD.
    [0008]
    8. Method according to one of claims 1 to 6, characterized in that said pattern B corresponds to x'T with x 'selected according to option B2), x' being the MXD.
    [0009]
    9. Method according to one of claims 1 to 6, characterized in that said pattern B corresponds to a linear aliphatic diamine according to option B3).
    [0010]
    10. Method according to one of claims 1 to 6, characterized in that the patterns A and B are selected as follows: for the pattern A being 9T, said pattern B is selected from: 10T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 30 to 45% - for the pattern A being 10T, said pattern B is selected from: 9T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD And MXD.T, preferably 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 25 at 45% - for the pattern A being 11T, said pattern B is selected from: 9T, 10T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 9T, 13T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 4 5% for the pattern A being 12T, said pattern B is selected from: 9T, 10T, 11T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, preferably 9T, 10T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 45%.
    [0011]
    Method according to claim 10, characterized in that the pattern A is a 9T pattern and the pattern B is selected from: 10T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD T, preferably 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 30 to 45; %.
    [0012]
    Method according to claim 10, characterized in that the pattern A is a 10T pattern and the pattern B is selected from: 9T, 11T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD T, preferably 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T, more preferably MPMD.T or MXD.T and MXD.T with a molar ratio of B ranging from 25 to 45%.
    [0013]
    Method according to claim 10, characterized in that the pattern A is an 11T pattern and the pattern B is selected from: 9T, 10T, 12T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD T, preferably 9T, 13T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 45%.
    [0014]
    14. A method according to claim 10, characterized in that the pattern A is a pattern 12T and the pattern B is selected from:, 10T, 11T, 13T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD. T, preferably 9T, 10T, 14T, 15T, 16T, 17T and 18T, MPMD.T and MXD.T, more preferably MPMD.T or MXD.T, with a molar ratio of B ranging from 20 to 45%.
    [0015]
    15. Method according to one of claims 7 to 14, characterized in that part of the pattern B which is up to 70%, preferably less than 40 mol% relative to B, is replaced by a pattern C and / or D as defined according to one of claims 1 to 3.
    [0016]
    16. Method according to one of claims 1 to 15, characterized in that said polyamide composition is a non-reactive composition according to b).
    [0017]
    17. Method according to one of claims 1 to 15, characterized in that said polyamide composition is a reactive prepolymer composition according to a) and precursor of said polyamide polymer of said matrix of the material.
    [0018]
    18. Process according to claim 17, characterized in that the said composition a) comprises or consists of at least one reactive prepolymer carrying on the same chain two terminal functions X 'and Y', respectively coreactive functions to each other by condensation, with X 'and Y' being amine and carboxy or carboxy and amine respectively.
    [0019]
    19. A method according to claim 17, characterized in that said reactive composition a) comprises at least two polyamide prepolymers reactive with each other and each having two identical terminal functions X or Y 'respectively, said function X' of a prepolymer being able to react only with said function Y1 of the other prepolymer, in particular by condensation, more particularly with X 'and Y' being amine and carboxy or carboxy and amine respectively
    [0020]
    20. Process according to claim 17, characterized in that said composition a) or precursor composition, comprises or consists of: a1) at least one prepolymer of said thermoplastic polyamide polymer carrying n terminal reactive functions X, chosen from: -NF -I2, -CO2H and -OH, preferably NH2 and -CO2H with n being 1 to 3, preferably 1 to 2, more preferably 1 or 2, more particularly 2 a2) at least one YNY chain extender, with A being a hydrocarbon-based biradical, of non-polymeric structure, carrying 2 identical Y terminal reactive functional groups reactive by polyaddition with at least one X function of said prepolymer a1), preferably with a molecular mass of less than 500, more preferably less than 400.
    [0021]
    21. Method according to one of claims 17 to 20, characterized in that said reactive prepolymers of said composition a) have a number average molecular weight Mn ranging from 500 to 10000, preferably from 1000 to 6000.
    [0022]
    22. Process according to one of claims 17 to 21, in which X is NH 2 or OH, in particular NH 2 and Y is chosen from an oxazinone and an oxazolinone.
    [0023]
    23. The method according to one of claims 17 to 21, wherein X is CO2H and Y is selected from epoxy and oxazoline.
    [0024]
    24. The process as claimed in claim 23, characterized in that X is CO2H and Y-A'-Y is chosen from phenyl bis oxazolines, preferably 1,3-phenylenebis (2-oxazoline) or 4-phenylenebis (2-oxazoline) (PBO).
    [0025]
    25. Method according to one of claims 1 to 24, characterized in that it comprises at least one polymerization step of at least one reactive composition a) as defined according to one of claims 17 to 24 or a step molding or implementation of at least one non-reactive composition b) as defined in claim 16, or a stage of extrusion implementation of at least one non-reactive composition b) as defined according to the claim 16.
    [0026]
    26. The method of claim 25, characterized in that it comprises the following steps i) injection of a composition as defined according to one of claims 1 to 24 24 without fibrous reinforcement in an open mold or closed or out mold, polymerization reaction in the case of a reactive composition a) polyamide according to one of claims 17 to 24, by heating said composition of step i) with chain extension, as the case may be, by reaction of polycondensation or by polyaddition reaction, in bulk in the molten state, with in the case of polycondensation, a vacuum removal of condensation products when it is a closed mold, using a system vacuum extraction, otherwise and preferably with the polycondensation being carried out in open mold or out of mold, iii) an implementation or molding of said composition of step i) in the case of a non-reactive polyamide composition b) for fo the final part in a mold or with another implementation system and, in the case of a reactive composition a), a step of molding or other implementation and simultaneously with the step ii) of polymerization.
    [0027]
    27, Method according to claim 26, characterized in that said implementation is carried out according to a RIM process, injection-compression, in particular in the case of a reactive composition a).
    [0028]
    28. The method of claim 25, characterized in that it comprises the following steps: i) polymerization reaction in the case of a reactive composition a) polyamide according to one of claims 17 to 24, by heating said composition of step i) with chain extension, as the case may be, by polycondensation reaction or by bulk melt polyaddition reaction, in the case of polycondensation, vacuum removal of the condensation products with the aid of a vacuum extraction system to obtain a non-reactive composition, extrusion of the non-reactive composition resulting from stage i) or of a non-reactive composition as defined according to one of claims 1 at 24 without fibrous reinforcement,
    [0029]
    29. Use of a composition as defined in one of claims 1 to 24 or a non-reactive polymer as defined in said composition b) or a polymer obtainable from a reactive composition such as defined according to said composition a), for the manufacture of mechanical parts, based on said composite material, single-layer or multilayer pipe, or film, 30. Use according to claim 29, characterized in that said mechanical parts of said material relate to applications in the field of the automobile, electrical or electronic, railway, marine, wind, photovoltaic, solar, including solar panels and components of solar power plants, sports, aeronautics and space, road transport (regarding trucks), building, civil engineering, billboards and recreation. 31. Use according to claim 30, characterized in that said mechanical parts for applications in the automobile are parts under the engine cover for the transport of fluid, in particular in air intake devices, cooling (for example by air, coolant), transport or transfer of fuels or fluids (such as oil, water). 32. Use according to claim 30, characterized in that said mechanical parts for applications in the electrical or electronic are goods of electrical and electronic equipment, such as encapsulated solenoids, pumps, telephones, computers, printers, fax machines, modems, monitors, remote controls, cameras, circuit breakers, electrical cable ducts, fiber optics, switches, multimedia systems. 33. Thermoplastic material characterized in that it results from the use of at least one composition for thermoplastic material as defined in one of claims 1 to 24. 34. Mechanical part of thermoplastic material, characterized in that it results from the use of at least one composition as defined according to one of claims 1 to 24 or from the use of a non-reactive polyamide polymer as defined according to said composition b) or a polymer capable of be obtained from a reactive composition as defined according to said composition a) or that it is based on a material as defined according to claim 33 or that it is obtained by a process as defined according to one of claims 25 to 28. 35. Part according to claim 34, characterized in that it is mechanical parts for applications in the automobile such as parts under the engine hood for the transport of fluid , in particular in air intake devices, cooling (for example by air, coolant), transport or transfer of fuels or fluids (such as oil, water). 36. Part according to claim 34, characterized in that it is mechanical parts for applications in the electrical or electronics such as electrical and electronic equipment, such as encapsulated solenoids, pumps, telephones. , computers, printers, fax machines, modems, monitors, remote controls, cameras, circuit breakers, electrical cable ducts, fiber optics, switches, multimedia systems.
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    同族专利:
    公开号 | 公开日
    EP3131946A1|2017-02-22|
    JP6731853B2|2020-07-29|
    US20170044317A1|2017-02-16|
    WO2015159014A1|2015-10-22|
    KR20160147264A|2016-12-22|
    US10344126B2|2019-07-09|
    KR102268482B1|2021-06-22|
    JP2019203129A|2019-11-28|
    JP2017517594A|2017-06-29|
    CN106414554B|2020-11-03|
    FR3019822B1|2017-10-20|
    CN106414554A|2017-02-15|
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    法律状态:
    2016-03-09| PLFP| Fee payment|Year of fee payment: 3 |
    2017-03-13| PLFP| Fee payment|Year of fee payment: 4 |
    2018-03-15| PLFP| Fee payment|Year of fee payment: 5 |
    2020-03-12| PLFP| Fee payment|Year of fee payment: 7 |
    2021-03-10| PLFP| Fee payment|Year of fee payment: 8 |
    优先权:
    申请号 | 申请日 | 专利标题
    FR1453347A|FR3019822B1|2014-04-15|2014-04-15|PROCESS FOR PRODUCING A THERMOPLASTIC MATERIAL BASED ON SEMI-CRYSTALLINE POLYAMIDE|FR1453347A| FR3019822B1|2014-04-15|2014-04-15|PROCESS FOR PRODUCING A THERMOPLASTIC MATERIAL BASED ON SEMI-CRYSTALLINE POLYAMIDE|
    US15/304,563| US10344126B2|2014-04-15|2015-04-14|Method for manufacturing a thermoplastic material made from semi-crystalline polyamide|
    JP2016562836A| JP6731853B2|2014-04-15|2015-04-14|Method for producing a thermoplastic material made from semi-crystalline polyamide|
    EP15720382.9A| EP3131946A1|2014-04-15|2015-04-14|Method for manufacturing a thermoplastic material made from semi-crystalline polyamide|
    KR1020167031673A| KR102268482B1|2014-04-15|2015-04-14|Method for manufacturing a thermoplastic material made from semi-crystalline polyamide|
    CN201580031694.8A| CN106414554B|2014-04-15|2015-04-14|Method for producing thermoplastic materials made of semi-crystalline polyamide|
    PCT/FR2015/050996| WO2015159014A1|2014-04-15|2015-04-14|Method for manufacturing a thermoplastic material made from semi-crystalline polyamide|
    JP2019110844A| JP2019203129A|2014-04-15|2019-06-14|Method for manufacturing thermoplastic material made from semi-crystalline polyamide|
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