Patent Application
20240318055
The present invention relates to a resin film comprising a layer of polymerisable resin. The present invention also relates to a method of manufacturing a fibre-reinforced composite material using such a resin film. In particular, the present invention relates to resin films for manufacturing fibre-reinforced composite materials in which a solid resin film can be used to provide a curable resin for combining with a fibrous reinforcement material, instead of the use of prepregs or a liquid resin infusion process.
It is well known in the art of manufacturing fibre-reinforced composite materials to combine a curable resin with fibrous reinforcement material in a mould prior to curing the resin. It is also well known that two alternative known processes may be used to achieve such a combination, in particular the use of prepregs or a liquid resin infusion process.
Prepregs comprise a fibrous reinforcement material which has previously been impregnated with a desired quantity of resin to provide a pre-set weight ratio between the fibres and the resin, and the resin is in a substantially solid form, and typically has been partly cured so as to be “B-staged” and thereby exhibit an increased viscosity. The prepregs are laid up in the mould, and then the resin is heated, to cause the resin to liquefy and thereby flow to wet-out the fibres, and then the resin is subsequently cured.
A liquid resin infusion process provides dry fibrous reinforcement material in the mould, and then liquid resin is introduced into the mould, typically under vacuum in a process called vacuum assisted resin transfer moulding (VARTM), to wet-out the fibres, and then the resin is subsequently cured.
These known processes may be used for manufacturing large mouldings, such as wind turbine blades and marine parts such as boat hulls.
As a general rule, for manufacturing such large mouldings, prepregs provide the advantage of increased control of the distribution of the resin as compared to a liquid resin infusion process, but have the disadvantage of increased material cost.
Historically, wind turbine blades have been manufactured using either prepregs or a liquid resin infusion process. Currently, wind turbine blade producers are increasingly moving away from the use of prepregs to the use of liquid infusion of an epoxy resin. The primary reason is cost reduction. However, liquid infusion brings several disadvantages, for example increased parasitic resin weight, undesired resin uptake by the core of the blade, and a higher risk of product or manufacturing failure.
For the manufacture of large marine parts, such as boat hulls, currently boat manufacturers typically using polyester or vinyl ester resins in wet-layup processes. However, the mechanical performance of such resins is generally low compared to the mechanical performance of epoxy resins. Also, these resins exhibit poor safety performance during fabrication, for example by emitting fumes. The alternative use of epoxy resin prepregs would increase manufacturing cost, and may require the need to procure new higher temperature tooling and oven systems.
Consequently, there is a need to provide an improved resin system for the manufacture of fibre-reinforced composite materials, in particular large parts such as wind turbine blades and marine parts such as boat hulls, which can provide the combination of ease of manufacture, low manufacturing cost with regard to materials and manufacturing apparatus, and good mechanical performance of the resultant composite material product.
As an alternative process which has nevertheless not been known for the manufacture of large composite parts, the construction of composite material laminates using solid resin films layered with dry reinforcement is historically known. The resin films comprise a single component resin, known in the art as a “1K” resin. However, there is no disclosure of such resin films which can reliably be used to manufacture large composite material parts, as discussed above.
The present invention aims to provide a solid resin film which has particular use in the manufacture of large composite material parts and structures.
The present invention aims to provide a solid resin film which can provide the combination of ease of manufacture, low manufacturing cost with regard to materials and manufacturing apparatus, and good mechanical performance of the resultant composite material product, and in particular can provide improved performance as compared to the use of prepregs or liquid resin infusion for the manufacture of large composite material parts and structures.
The present invention aims to provide a solid resin film, and an associated method of manufacturing fibre-reinforced composite materials, in which the solid resin film can be used to provide a curable resin for combining with a fibrous reinforcement material, instead of the use of prepregs or a liquid resin infusion process, in particular for the manufacture of large composite material parts and structures.
In a first aspect, the present invention provides a resin film comprising a layer of polymerisable resin which is in the form of a solid layer at 20° C., at least 50 wt % of the polymerisable resin comprising at least one polymerisable vinyl ester prepolymer having at least two carbon-carbon unsaturated functional groups, the prepolymer being polymerisable by reaction of the unsaturated functional groups to form a cured resin, wherein the polymerisable resin further comprises a curing system for polymerizing the polymerisable vinyl ester prepolymer, wherein the at least one polymerisable vinyl ester prepolymer comprises at least one prepolymer which is present in a concentration of at least 10 wt %, based on the weight of the polymerisable resin, and has the structure R1n-R2-R1′m, wherein R1 and R1′ are the same or different, n and m are each at least one and may be the same or different, and each of R1 and R1′ includes a carbon-carbon unsaturation at a free end thereof remote from R2, and includes a residue of an epoxy resin, and wherein R2 is a polyfunctional chain extending linker between R1 and R1′, and is derived from a polyfunctional carboxylic acid having the structure R—Fnx, where Fn is a carboxylic acid functional group, x is at least 2, and R comprises an organic moiety having aliphatic, araliphatic, cycloaliphatic, heterocyclic and/or aromatic groups, containing any type and/or combination of saturated, unsaturated and/or aromatic carbon bonds, and wherein R may be unsubstituted or substituted by functional groups and/or heteroatoms.
In a second aspect, the present invention provides a resin film comprising a layer of polymerisable resin which is in the form of a solid layer at 20° C., at least 50 wt % of the polymerisable resin comprising at least one polymerisable vinyl ester prepolymer having at least two carbon-carbon unsaturated functional groups, the prepolymer being polymerisable by reaction of the unsaturated functional groups to form a cured resin, wherein the polymerisable resin further comprises a free-radical curing system for polymerizing the polymerisable vinyl ester prepolymer, wherein the free-radical curing system comprises at least one peroxide curing agent having a self-accelerating decomposition temperature within the range of from 45 to 95° C., wherein the at least one peroxide curing agent is present in a concentration of from 0.1 to 3 parts per hundred based on the weight of the polymerisable vinyl ester prepolymer.
In a third aspect, the present invention provides a resin film comprising a layer of polymerisable resin which is in the form of a solid layer at 20° C., at least 50 wt % of the polymerisable resin comprising at least one polymerisable vinyl ester prepolymer having at least two carbon-carbon unsaturated functional groups, the prepolymer being polymerisable by reaction of the unsaturated functional groups to form a cured resin, wherein the polymerisable resin further comprises a curing system for polymerizing the polymerisable vinyl ester prepolymer, wherein the polymerisable resin in the resin film, the polymerisable resin additionally comprising the curing system, has (i) a cold Tg of from −10 to 15° C., measured using a dynamic oscillatory measurement within a temperature range of −10 to 40° C. at a ramp rate of 2° C./minute, (ii) a phase angle (δ) Tonset delta between a storage modulus and a loss modulus of from −5 to 15° C., measured using a dynamic oscillatory measurement within a temperature range of −10 to 40° C. at a ramp rate of 2° C./minute, and (iii) a storage modulus and a loss modulus which are equal within a temperature range of from 70 to 110° C., measured using a dynamic oscillatory measurement within a temperature range of 30 to 130° C. at a strain of 0.125%, and ramp rate of 1° C. A suitable machine for such testing to determine these rheological properties of Cold Tg, phase angle, storage modulus and loss modulus is a TA Instruments AR2000 rheometer, fitted with a 20 mm steel plate geometry and Peltier temperature control system.
In a fourth aspect, the present invention provides a method of manufacturing a fibre-reinforced composite material, the method comprising:
The preferred embodiments of the present invention can provide a resin film which is in the form of a solid layer at 20° C., and an associated method of manufacturing fibre-reinforced composite materials which causes the resin film to melt and flow into a layer of fibrous reinforcement material thereby to wet-out the fibres in the fibrous reinforcement material, i.e. an infusion process, which can achieve the process and performance advantages of the use of prepregs but at a low material cost substantially corresponding to the cost of a liquid resin infusion process, and with the additional benefits of faster cycle times as compared to a typical liquid resin infusion process.
For the manufacture of large marine parts, the preferred embodiments of the present invention can further provide the advantage that volume boat producers typically currently using polyester or vinyl ester wet-lay processes can readily modify the production process to achieve increased product performance with regard to mechanical properties, similar to the performance achievable by epoxy resin prepregs, but without the increase in cost or the need to procure new higher temperature tooling and oven systems that would be required with the use of prepregs.
Embodiments of the present invention will now be described by way of example only, with reference to the accompanying drawings, in which:
The drawings of
Referring to
The alternate layering of a solid resin film and fibrous reinforcing material to form an alternating laminate structure distinguishes the method of manufacturing a fibre-reinforced composite material from the use of solid prepregs and the infusion of a liquid resin, from outside the mould cavity, into a stack of dry fibrous reinforcement material.
The resin film 2 is in the form of a solid layer, which is solid at 20° C., and typically solid over a broad temperature range which includes the typical ambient or room temperature value of 20° C. and encompasses a working range for use of the resin film 2 in the manufacturing method. Typically, the resin film is solid at temperatures up to 40° C.
Typically, during the method the resin film 2 is heated to a temperature above the melting temperature of the resin to form a liquid which then flows to wet-out the fibres of a fibrous reinforcement material. Then the resin is cured to form a cured resin matrix containing the fibrous reinforcement material. This forms a fibre-reinforced resin matrix composite material during the moulding of large composite part, for example a wind turbine blade or a marine vessel.
As shown in
The resin film 2 is provided in the form of a wound roll 8 of an elongate length of the resin film 2. The resin film 2 is unwound from the roll 8 and laid over the surface of a layer of fibrous reinforcement material 6. The weight per unit area, and therefore the thickness, of the resin film 2 is selected to provide the desired weight ratio between the fibrous reinforcement material 6 and the cured resin in the resultant fibre-reinforced composite material.
In one embodiment, the resin film 2 is a coherent layer having first and second opposed resin surfaces 11, 13. The first and second opposed resin surfaces 11, 13 may be self-adhesive, which means that the surface have an intrinsic tack at the lay-up temperature, so that the resin adheres to the surface of the layer of fibrous reinforcement material 6. Such a resin film 2 may be provided in roll form with the successive layers of the resin film 2 in the roll 8 being in contact with each other.
As known to those skilled in the art, the degree of tack of a polymerisable resin can be controlled. Consequently, the tack may be controlled so that the roll 8 of the resin film 2 can readily be unwound.
In one embodiment, the resin film 2 is temporarily supported by a release backing layer 12, for example a siliconised paper or polymer layer, and one of the opposed resin surfaces is releasably adhered to the release backing layer 12. The resin film 2 is separated from the release backing layer 12 when the roll 8 is unwound to deliver the resin film 2 into the mould 4.
In some embodiments of the present invention, the resin of the resin film 2 has sufficient intrinsic tear strength that the resin film can be completely coherent and unsupported when delivered into the mould 4. The resin film 2 is preferably formulated to have sufficient tensile strength and tear strength so as not to distort or break during the end application to manufacture the composite material part.
However, in other embodiments of the present invention, in order to increase the tear strength, a very lightweight fibrous tissue or scrim may be co-laminated into the resin film 2. The fibrous tissue or scrim can provide the desired tear strength, without reducing other material or performance properties, or significantly increasing material cost.
Accordingly, in some embodiments, as shown in detail in
The lightweight textile sheet 14 may comprise woven or non-woven polymeric fibres, for example polyester fibres. The material and areal weight of the lightweight textile sheet 14 are typically selected so as to provide substantially no modification to the mechanical properties of the resultant fibre-reinforced composite material. The lightweight textile sheet 14 is provided to enhance the tear strength of the resin film 2. The desired tear strength depends upon the specific manufacturing application and typically the dimensions of the component or structure to be manufactured.
Therefore, the resin film 2 is positioned adjacent to the layer of fibrous reinforcement material 6 to form a laminate 10 between the resin film 2 and the layer of fibrous reinforcement material 6. After the layer of the resin film 2 has been laid over the surface of the layer of fibrous reinforcement material 6, a subsequent layer of fibrous reinforcement material 6 is laid over the resin film 2. This sequence of steps is repeated so that a laminated stack 15 of alternating plies of fibrous reinforcement material 6 and resin film 2 is built up in the mould 4 until the desired total fibre weight, with the desired proportions by weight of fibrous reinforcement material and resin, has been achieved.
Then the mould 4 is then typically closed to contain the laminated stack 15 within the mould cavity 17. Thereafter, the temperature of the laminated stack 15 is increased to an elevated temperature to cause the polymerisable resin to melt and flow into the layers of fibrous reinforcement material 6 thereby fully to wet out the fibres in the fibrous reinforcement material 6.
Subsequently, the resin thereby dispersed uniformly throughout the mould cavity 17 is subjected to a polymerizing step in which the monomer is polymerized at a curing temperature, which is at least as high as the elevated temperature to wet-out the fibres, to form a cured resin matrix containing the fibrous reinforcement material 6.
Typically, the mould 4 is heated to a first elevated temperature, and optionally held at that temperature for a dwell time period, to cause complete wet-out of the fibres in the fibrous reinforcement material by the liquefied molten resin. During or prior to the heating, the laminate is consolidated with pressure or vacuum to ensure complete wet-out of the fibres. Thereafter, the mould 4 is heated to a second elevated temperature, which is higher than the first elevated temperature, which is a curing temperature. Preferably, the polymerization step is carried out by radical curing of unsaturated functional groups in the polymerisable resin by a free-radical curing system in the initial resin film 2. Typically, a peroxide radical curing is used to cure the unsaturated functional groups in the polymerisable resin. The mould 4 is then held at the curing temperature for a sufficient curing time period, to cause complete curing of the polymerisable resin.
Preferably, for the manufacture of large parts and structures such as wind turbine blades and marine vessels, the curing system is selected to exhibit a peak exotherm temperature within a desired temperature range. The peak exotherm temperature of any given curing system may be defined relative to the curing of a standard polymerisable resin having a specific monomer composition.
In particular, the curing system preferably exhibits a peak exotherm temperature of from 80 to 160° C., more preferably from 100 to 140° C., when evaluated via differential scanning calorimetry (DSC) to cure a model polymerisable resin consisting of a known commercially available methacrylate in place of the vinyl ester resin, used at equivalent parts by weight. In particular the model polymerisable resin consists of 2-hydroxyethyl methacrylate (also known as HEMA or BISOMER HEMA), having CAS number: 868-77-9) containing inhibitor MEHQ (4-methoxyphenol) at a concentration of 200 ppm by weight. Dynamic DSC evaluation of the curative system in the commercially available methacrylate BISOMER HEMA, is carried out over a temperature range of from 25 to 260° C. at a ramp rate of 10° C./min. A suitable machine for such DSC analysis is sold under the trade name “DSC 20” by TA Instruments, which uses a sample size, i.e. a total weight of the 2-hydroxyethyl methacrylate and the free-radical curing system, of from 8 to 16 mg, is suitable the DSC analysis is carried out with the sample under a nitrogen environment. In the DSC evaluation using the model polymerisable resin, the free-radical curing system comprises at least one peroxide curing agent which is present in a total peroxide curing agent concentration of from 0.1 to 3 parts per hundred based on the weight of the 2-hydroxyethyl methacrylate.
As shown in
As shown in
A similar production process may be used for other parts and structures to be moulded, in particular large parts such as marine vessels and structural parts therefor. When a boat hull is to be manufactured, the intrinsic tack of the resin film may assist in adhering the resin film to non-horizontal, even vertical, surfaces, of the fibrous reinforcement material or the mould, during the lay-up process.
It may readily be seen from
In accordance with the preferred embodiments of the present invention, the resin film 2 comprises a layer of polymerisable resin which is in the form of a solid layer at 20° C.
As used herein, the term “solid” refers to a conventional solid state material as distinguished from a liquid or gas and intends to include those materials known as semi-solids, or flowable solids. The term semi-solid or flowable-solid is used herein to denote the mechano-physical state of a material that is flowable under moderate stress. More specifically, the semi-solid material should have a complex viscosity between about 10,000 and 3,000,000 cps, especially between about 50,000 and 500,000 cps, measured using a rheometer at a strain of 0.125% and 1 Hz oscillation with a 25 mm parallel plate geometry and 1 mm gap.
At least 50 wt % of the polymerisable resin comprises at least one polymerisable vinyl ester prepolymer having at least two carbon-carbon unsaturated functional groups. The prepolymer is polymerisable by reaction of the unsaturated functional groups to form a cured resin.
In the preferred embodiments of the present invention, the at least one polymerisable vinyl ester prepolymer comprises at least one prepolymer which is present in a concentration of at least 10 wt %, based on the weight of the polymerisable resin, and has the structure R1n-R2-R1′m, wherein R1 and R1′ are the same or different, n and m are each at least one and may be the same or different, and each of R1 and R1′ includes a carbon-carbon unsaturation at a free end thereof remote from R2, and includes a residue of an epoxy resin. R2 is a polyfunctional chain extending linker between R1 and R1′. R2 is derived from a polyfunctional carboxylic acid having the structure R—Fnx, where Fn is a carboxylic acid functional group, x is at least 2, and R comprises an organic moiety having aliphatic, araliphatic, cycloaliphatic, heterocyclic and/or aromatic groups, containing any type and/or combination of saturated, unsaturated and/or aromatic carbon bonds, and wherein R may be unsubstituted or substituted by functional groups and/or heteroatoms.
Preferably, R2 is derived from a polyfunctional carboxylic acid selected from the group consisting of malic acid, tartaric acid, phenylsuccinic acid, 2-aminooctanedioic acid, phthalic acid, adipic acid, dodecanedioic acid, citric acid, trimesic acid, aconitic acid and mellitic acid.
More preferably, R2 is derived from a di-carboxylic acid selected from the group consisting of malic acid, tartaric acid, phenylsuccinic acid, 2-aminooctanedioic acid, phthalic acid, adipic acid and dodecanedioic acid. In a particularly preferred embodiment, R2 is derived from phthalic acid.
In the preferred embodiments of the present invention, R2 is a di-carboxylic acid containing no additional heteroatoms having a carbon backbone comprising less than <30 carbon atoms. Typically, the carbon backbone comprises ≥10 carbon atoms and comprises unsaturated and/or aromatic carbon bonds in the carbon backbone.
In the preferred embodiments of the present invention, in R1 and R1′ the residue is preferably of a bisphenol epoxy resin, and more preferably comprises a residue of a bisphenol A epoxy resin.
Preferably, each of R1 and R1′ comprises the structure A-B—, where A includes the carbon-carbon unsaturation in a moiety derived from an acrylate or methacrylate group, and B is a moiety derived from a bisphenol epoxy resin, and in R1 each A and/or B may be the same as or different from the A and/or B in R1′.
In some preferred embodiments, A comprises the residue of a reaction product between a first reactant comprising an acrylate or methacrylate group and a second reactant comprising a dianhydride having an aliphatic, araliphatic, cycloaliphatic, heterocyclic or aromatic moiety.
As described above, at least 50 wt % of the polymerisable resin comprises at least one polymerisable vinyl ester prepolymer having at least two carbon-carbon unsaturated functional groups, the prepolymer being polymerisable by reaction of the unsaturated functional groups to form a cured resin. Furthermore, the at least one polymerisable vinyl ester prepolymer comprises at least one prepolymer which is present in a concentration of at least 10 wt %, based on the weight of the polymerisable resin which has the structure R1n-R2-R1′m. In other words, at least a proportion of the polymerisable resin comprises one or more polymerisable vinyl ester prepolymers which (i) have at least two carbon-carbon unsaturated functional groups but (ii) do not have has the structure R1n-R2-R1′m. These additional polymerisable vinyl ester prepolymer(s) can be co-polymerized with the at least one prepolymer which has the structure R1n-R2-R1′m, and may have a molecule structure between the unsaturated functional groups which may be selected from a variety of alternative structures.
In particular, in some preferred embodiments of the present invention, the polymerisable resin comprises a mixture of at least one first polymerisable vinyl ester prepolymer having the structure R1n-R2-R1′m and at least one second polymerisable vinyl ester prepolymer having the structure A-B-A, where A includes the carbon-carbon unsaturation in a moiety derived from an acrylate or methacrylate group, and B is a moiety derived from an epoxy resin, typically a bisphenol epoxy resin. Typically, A comprises the residue of a reaction product between a first reactant comprising an acrylate or methacrylate group and a second reactant comprising a dianhydride having an aliphatic, araliphatic, cycloaliphatic, heterocyclic or aromatic moiety, the first and second polymerisable vinyl ester prepolymers.
In other words, in a preferred embodiment the second polymerisable vinyl ester prepolymer has a molecular structure similar to that of the first polymerisable vinyl ester prepolymer, except that the second polymerisable vinyl ester prepolymer does not include a polyfunctional chain extending linker R2, and only includes a single residue or moiety derived from an epoxy resin, typically a bisphenol epoxy resin. In the cured resin of the preferred embodiment, the polymer molecular network comprises the first and second polymerisable vinyl esters cured together, and a proportion of the cured vinyl esters include the polyfunctional chain extending linker R2 to provide the desired rheological properties to the resin film. The at least one first polymerisable vinyl ester prepolymer and the at least one second polymerisable vinyl ester prepolymer are present in a molecular ratio of Z:1, preferably wherein Z is up to 0.5, more preferably wherein Z is within the range of from 0.1 to 0.5.
In the preferred embodiments of the present invention, the polymerisable vinyl ester prepolymer has a heat of polymerization of from 110 to 150 KJ/kg, preferably from 120 to 140 KJ/kg, more preferably from 125 to 135 KJ/kg, typically about 130 KJ/kg.
Preferably, the polymerisable vinyl ester prepolymer has a theoretical average, by number, molecular weight of from 750 to 1250, for example from 800 to 1100.
Preferably, the polymerisable vinyl ester prepolymer has less than 2.2 gram equivalents of unsaturation per kilogram of the polymerisable vinyl ester prepolymer.
The polymerisable resin further comprises a curing system, which is preferably a free-radical curing system for polymerizing the polymerisable vinyl ester prepolymer. In the preferred embodiments of the present invention, the free-radical curing system comprises at least one peroxide curing agent having a self-accelerating decomposition temperature (SADT) within the range of from 45 to 95° C. More preferably, the self-accelerating decomposition temperature is within the range of from 50 to 80° C., for example from 55 to 70° C.
Preferably, the at least one peroxide curing agent is present in a concentration of from 0.1 to 3 parts per hundred based on the weight of the polymerisable vinyl ester prepolymer. Preferably, the at least one peroxide curing agent is present in a concentration of from 0.5 to 5 parts per hundred, for example from 0.5 to 1.5 parts per hundred, based on the weight of the polymerisable vinyl ester prepolymer.
In the preferred embodiments of the present invention, the at least one peroxide curing agent is selected from tert-butoxy 2-ethylhexyl carbonate, 2-Butanone peroxide (methyl ethyl ketone peroxide), dibenzoyl peroxide, cyclohexylidenebis[tert-butyl] peroxide, cyclohexylidenebis[tert-amyl] peroxide, cumene hydroperoxide, tert-butylperoxy isopropyl carbonate, tert-butyl peroxybenzoate, tert-butyl peroxy-3,5,5-trimethylhexanoate, 1,1-di(tert-butylperoxy)-3,3,5-trimethylcyclohexane, tert-amyl peroxy-2-ethylhexyl carbonate, di-tert-butyl peroxide, tert-amyl peroxybenzoate, di-tert-amyl peroxide, N-Butyl-4,4-di(tert-butylperoxy)valerate, 1,2-dimethylproplyidene dihydroperoxide and methyl isopropyl ketone peroxide or any mixture of two or more thereof.
Examples of peroxide curing agents that may be used in accordance with the present invention are listed in Table 1.
In the preferred embodiments of the present invention, the free-radical curing system further comprises (i) a first auxiliary curing agent comprising a transition metal complex or a transition metal ligand and/or (ii) a second auxiliary curing agent comprising at least one of an aliphatic dione and a nitrogen-containing aliphatic or aromatic compound.
Typically, in the first auxiliary curing agent the transition metal comprises copper or iron.
One preferred first auxiliary curing agent is a copper complex comprising copper acetate and potassium neodecanoate, to provide copper ions with a neodecanoate ligand, in a solvent mixture. The solvent mixture may comprise diethylene glycol and diethanolamine. A suitable copper complex is sold under the trade mark Nouryact® CF12N (CAS Number 142-71-2) by Nouryon.
Another preferred first auxiliary curing agent is an iron complex comprising 2,2′-bipyridine as a ligand for iron ions in a solvent mixture. The solvent mixture may comprise diethylene glycol and diethanolamine. Suitable iron complexes are sold under the trade marks Nouryact® CF30 and Nouryact® CF40, and BORCHI® OXY-CURE, by Nouryon.
A further preferred first auxiliary curing agent is an iron complex comprising iron (1+), chloro[dimethyl-9,9-dihydroxy-3-methyl-2,4-di-(2-pyridylkN)-7-[(2-pyridinyl-kN)methyl]-3,7-diazabicyclo[3.3.1]nonane-1,5-dicarboxylate-kN3, kN7]-, chloride(1-). The iron complex may again be in a solvent, for example 2-hydroxy methacrylate. A suitable iron complex is sold under the trade name FeONIX C1-95 by Welychem Catexel and has CAS Number 478945-46-9. Another suitable iron complex is sold under the trade mark Nouryact® CF40 by Nouryon.
Preferably, the first auxiliary curing agent is present in a concentration of from 0.05 to 3.0 parts per hundred based on the weight of the polymerisable vinyl ester prepolymer, more preferably from 0.2 to 1 parts per hundred, for example from 0.2 to 0.6 parts per hundred.
Typically, the nitrogen-containing aliphatic or aromatic compound comprises a substituted or unsubstituted acetamide, aniline or toludine.
Preferably, the aliphatic dione comprises 2,4-pentane dione, ethyl acetoacetate, N,N-diethylacetoacetamide, 3-methyl-2,4-pentanedione, or 3-ethyl-2,4-pentanedione, or any mixture of any two or more thereof, and/or the nitrogen-containing aliphatic or aromatic compound comprises N,N-diethylacetoacetamide, 4,N,N-trimethyl aniline, N,N-diethylaniline or ethoxylated-para-toluidine, or any mixture of any two or more thereof.
Preferably, the second auxiliary curing agent is present in a concentration of from 0.05 to 3.0 parts per hundred based on the weight of the polymerisable vinyl ester prepolymer, more preferably from 0.1 to 3 parts per hundred, yet more preferably from 0.2 to 1 parts per hundred, for example from 0.2 to 0.6 parts per hundred.
In the preferred embodiments of the present invention, the free-radical curing system further comprises a curing inhibitor comprising a substituted benzene, optionally 10H-Phenothiazine.
Preferably, the curing inhibitor is present in a concentration of from 0.01 to 1.0 parts per hundred based on the weight of the polymerisable vinyl ester prepolymer, for example from 0.01 to 0.1 parts per hundred.
In the preferred embodiments of the present invention, the polymerisable resin has viscoelastic properties which enables the resin film 2 to be deposited as a solid layer onto a fibrous layer in a mould, and then upon heating readily and uniformly wet-out the fibrous layer prior to curing of the polymerisable resin.
For example. preferably the polymerisable resin in the resin film, the polymerisable resin additionally comprising the curing system, has a cold Tg of from −10 to 15° C., preferably from −5 to 5° C., measured using a dynamic oscillatory measurement within a temperature range of −10 to 40° C. at a ramp rate of 2° C./minute.
The preferred polymerisable resin has a phase angle (δ) Tonset delta between a storage modulus and a loss modulus of the polymerisable resin of −5 to 15° C., measured using a dynamic oscillatory measurement within a temperature range of −10 to 40° C. at a ramp rate of 2° C./minute. Preferably, the polymerisable resin has a storage modulus and a loss modulus which are equal within a temperature range of from 70 to 110° C., measured using a dynamic oscillatory measurement within a temperature range of 30 to 130° C. at a strain of 0.125% and ramp rate of 1° C.
Preferably, the polymerisable resin has a minimum viscosity within a temperature range of from 75 to 100° C., measured using a dynamic oscillatory measurement within a temperature range of 30 to 130° C. at a strain of 0.125% and ramp rate of 1° C.
Preferably, the at least one polymerisable vinyl ester prepolymer of the polymerisable resin, in the absence of any curing system for polymerizing the polymerisable vinyl ester prepolymer, has a viscosity within the range of 30 to 100 Poise, typically from 50-80 Poise, at a temperature of 85° C., measured using a CAP viscometer from AMETEK Brookfield at a shear rate of 0.5-12 s−1, which may be achieved using spindle 3 at a rotational velocity of 50 rpm for a run time of 20 seconds.
In the preferred embodiments of the present invention, the polymerisable resin is free of any particulate filler and/or free of any solvent for the at least one polymerisable vinyl ester prepolymer. Additionally or alternatively, in the preferred embodiments of the present invention, the polymerisable resin consists of the at least one polymerisable vinyl ester prepolymer and a free-radical curing system for polymerizing the polymerisable vinyl ester prepolymer.
The resin films of the preferred embodiments of the present invention have particular application to wind turbine blade construction and the fabrication of production boats. Although different performance, curing and handling characteristics are required for each different application, nevertheless the use of the resin film, to avoid the higher cost of prepregs and to avoid the processing difficulties of liquid resin infusion, apply to each application.
In accordance with the preferred embodiments of the present invention, the resin film is a self-curing 1K thermoset resin film. This can be supplied in solid form, for example in a roll, directly to the component fabricator.
The primary benefits of the use of a resin film in accordance with the preferred embodiments of the present invention include:
Depending on the resin chemistry other advantages may be realised including:
Preferably, the 1K resin films may be manufactured in a variety of different film weights for a fabricator to combine with a fabric and produce a laminate.
The resin film is also preferably formulated to have sufficient structure to prevent the resin inadvertently flowing during storage and transportation under the forces exerted when supplied in large rolls. Preferably, the resin molecular weight is increased or advanced to limit “cold flow”.
In accordance with the preferred embodiments of the present invention, the resin film comprises a styrene-free methacrylate resin cured with an accelerated peroxide curing agent provided short processing times and low material costs.
In addition, in accordance with the preferred embodiments of the present invention, the resin film exhibits increased cold flow resistance to provide dimensional stability when supplied as a roll of unreinforced resin. This may be achieved through acid modification during the base resin synthesis, which acts to increase the molecular weight, and therefore lower the tack and increase the cold flow resistance.
In accordance with the preferred embodiments of the present invention, the resin film exhibits reliable process stability, shelf life and curing by the use of the combination of a peroxide curing agent and accelerator(s) which are selected and used in concentrations to increase shelf life, even at high storage temperatures, yet provide rapid and low temperature curing, for example a curing time of from 1 to 2 hours at a curing temperature of 80° C.
In accordance with the preferred embodiments of the present invention, during use of the resin film, unlike the use of a prepreg system, the fibrous reinforcement is not pre-wet with matrix resin. In addition, the use of a radical curing agent for curing the polymerisable resin can ensure that the viscosity does not increase straight away when curing, providing a period of time for wet-out and “fibre washing” prior to viscosity increase and matrix gelation.
In accordance with the preferred embodiments of the present invention, the combination of the polymerisable resin and the radical curing agent for curing the polymerisable resin may be formulated to provide a medium temperature curing (e.g. about 100° C.) system to provide long ambient shelf life to eliminate the requirement for cold shipment and storage, which is typically required for prepregs. Alternatively, the combination of the polymerisable resin and the radical curing agent for curing the polymerisable resin may be formulated to provide a low temperature (e.g. about 70° C.) curing system to suit low temperature curing at the expense of ambient storage life.
Typically, the resin film in accordance with the preferred embodiments of the present invention exhibits one or more of the following properties:
The resin film is self-adhesive (i.e. has some tack) and is flexible, and has sufficient tear strength and tensile strength to be formed in a range of different film weights, for example from 20 to 1000 g/m2, and can be stored in a rolled format without distorting or tearing. The tack is sufficient to enable in-mould positioning of the resin film at the desired location.
The resin film has sufficient “shelf life” to remain stable for several months without the requirement to store in refrigerated environments. The storage does not distort or flow on the roll during storage, and can be stored in ambient conditions without gelation occurring.
The resin film can be laminated with glass, carbon or other fibre reinforcements to fabricate a composite laminate.
The resin can be subjected to an elevated temperature, for example greater than 60° C., during the filming step of the preparation of the resin film and the resin does not cure, or gel adversely during preparation of the film. Typically, the resin has a gel time of from 10 to 60 minutes, preferably from 25 to 45 minutes, at a temperature of 70° C., as measured with a 100 gram sample using the Tecam method. The chemistry used in the polymerisable prepolymer and curative system is solvent-free and volatile-free and free, or substantially free, of highly toxic chemicals such as CMRs (chemicals which are carcinogenic, mutagenic or toxic to reproduction) and SVHCs (chemicals which are designated substances of very high concern).
Upon exposure to heat and pressure, the resin lowers in viscosity to impregnate and wet-out the fibre reinforcement forming a composite structure. The reactivity of the resin system is such that it provides enough time and a sufficient low enough viscosity to allow this to happen without curing.
Once the reinforcement has been wet, the resin rapidly crosslinks to form a cured thermoset composite of sufficient thermal and mechanical properties for the intended applications including wind turbine blade and marine craft. Preferably, the resin has a reaction onset temperature within the range of from 70 to 125° C., more preferably from 80 to 100° C., as measured by dynamic scanning calorimetry (DSC) over a temperature range of from 25 to 260° C. at a ramp rate of 10° C./minute. The resin preferably has an enthalpy of from 100 to 200 Joules/gram, more preferably from 115 to 150 Joules/gram, as measured by dynamic scanning calorimetry (DSC) over a temperature range of from 25 to 260° C. at a ramp rate of 10° C./minute. The resin preferably exhibits a peak temperature upon curing within the range of from 90 to 130° C., more preferably from 110 to 120° C., as measured by dynamic scanning calorimetry (DSC) over a temperature range of from 25 to 260° C. at a ramp rate of 10° C./minute, under a nitrogen environment.
The speed of curing is sufficiently rapid to allow a reduction in manufacturing “cycle time” remaining economical (typically <2 hours depending on cure temperature, which is preferably below 100° C.).
The temperature of curing is sufficiently low, preferably below 100° C., for example a curing temperature of 80° C., to facilitate the use of low temperature tooling which is associated with lower tooling manufacturing and material costs, reduce energy consumption during cure and lower curing cycle times.
The present invention is further described with reference to the following non-limiting Examples.
The Applicant's earlier WO-A-2011/073111 discloses vinyl ester resins which are synthesised using a two-step process. In a first step 2-hydroxyethylmethacrylate (Hema) is reacted with phthalic anhydride to form Hema phthalate as shown by the reaction below:
Thereafter, in a second step the Hema phthalate is reacted with liquid bisphenol A epoxy resin as shown by the reaction below to produce a vinyl ester called herein “vinyl ester 1”:
When synthesised with stoichiometric quantities of reagents, this vinyl ester 1 was found to have a viscosity of 30-50 Poise at 85° C. (viscosity was measured for the resin alone) and a cold Tg, measured by DSC (for the resin alone without addition of the curing system), of from −5 to 0° C.
Vinyl ester 1, comprising a polymerisable vinyl ester prepolymer, was found to be unsuitable or formation as a resin film because the tack of the resin was too high and the flow-on-the-roll of the resin was too high.
It is believed by the present inventors that the excessively high tack and flow-on-the-roll properties, which prevent vinyl ester 1 from serving as a resin film in accordance with the present invention, is associated with the property of a low temperature value for the cold Tg of the vinyl ester resin. In other words, the present inventors believed that an increase on the value of the cold Tg is required in order to improve the tack and flow-on-the-roll properties.
However, increasing the cold Tg typically also increases resin viscosity, and if the resin viscosity is too high this would inhibit good fabric wet-out when making laminates.
The present inventors investigated various mechanisms to try to improve the properties of vinyl ester 1 by increasing the cold Tg value with the aim of providing a resin suitable for making a resin film having the desired properties.
In Comparative Example 2, vinyl ester 1 was subjected to an additional B-staging step by reacting vinyl ester 1 with a diisocyanate to make a modified polymerisable vinyl ester prepolymer, called herein “vinyl ester 2”.
The reaction scheme is below:
In this reaction scheme, the isocyanate functionalities of the diisocyanate link the vinyl ester 1 molecules at available hydroxyl groups by forming urethane groups. The molecule of vinyl ester 2 is chain-extended as compared to the molecule of vinyl ester 1.
However, it was found that although for vinyl ester 2 the value of the cold Tg (measured for the resin alone) was increased, nevertheless the resin viscosity at 85° C. (measured for the resin alone) also increased linearly with temperature, as shown in
Vinyl ester 2 was found to be unsuitable for use as a resin film, since the tack and flow-on-the-roll were still too high, or the viscosity was too high.
In Comparative Example 3, an alternative vinyl ester, called herein “vinyl ester 3” as compared to Comparative Example 1 was synthesised. As compared to Comparative Example 1, 15 wt % of the liquid bisphenol A epoxy resin was replaced with a solid epoxy resin, which is an advanced, higher molecular weight epoxy resin having an epoxy equivalent weight (EEW) of 325, n=1.3 and a viscosity of 60 Poise at 85° C., the solid epoxy resin being available from Nan Ya Electronic Materials Kunshan Corp. Ltd., China under the product code NPES-901.
As shown in
In Comparative Example 4, an alternative vinyl ester, called herein “vinyl ester 4” as compared to Comparative Example 1 was synthesised. As compared to Comparative Example 1, 15 wt % of the liquid bisphenol A epoxy resin was replaced with a solid novolac epoxy resin having an epoxy equivalent weight (EEW) of 224 and a viscosity of 90 Poise at 85° C.
Vinyl ester 4 was synthesised according to the following reaction scheme shown below:
The resultant mixture of vinyl ester 1 with vinyl ester 4 provided a mixed polymerisable resin prepolymer system, called herein “vinyl ester 5”. The cold Tg (measured for the resin alone) and resin viscosity at 85° C. (measured for the resin alone) of vinyl ester 5 were acceptable, as shown in
In Comparative Example 4, vinyl ester 1 was subjected to an additional B-staging step by reacting vinyl ester 1 with a diisocyanate to make a modified polymerisable vinyl ester prepolymer, called herein “vinyl ester 2”.
In Comparative Example 5, an alternative vinyl ester, called herein “vinyl ester 6” as compared to Comparative Example 1 was synthesised. As compared to Comparative Example 1, in the second step of the synthesis of vinyl ester 1, in which Hema phthalate is reacted with the liquid bisphenol A epoxy resin, a portion of the Hema phthalate was replaced by phthalic anhydride, which is di-functional, can react with the epoxide groups, and functions as an in-situ chain extender during the second step of the synthesis.
Vinyl ester 6 was synthesised according to the following reaction scheme shown below:
The resultant vinyl ester 6 provided a polymerisable resin prepolymer for which the cold Tg (measured for the resin alone) and resin viscosity at 85° C. (measured for the resin alone) were acceptable, as shown in
In accordance with at least one aspect of the present invention, the molecular weight of a vinyl ester polymerisable prepolymer is increased by chain extending the monomer in situ using a specific polyfunctional chain extending linker.
In particular, it has been unexpectedly found by the present inventors that a polyfunctional chain extending linker which is derived from a polyfunctional carboxylic acid, having at least two functional groups capable of reacting with the epoxide groups, can provide a polymerisable resin prepolymer which is suitable for use to form a resin film. The use of such a polyfunctional chain extending linker has been found to provide unexpectedly high stability in a high viscosity resin, and in particular has been found to a sufficiently high viscosity and controllable tack so that a resin film can be formed, which can be formed as a roll, and the resin can achieve a stable viscosity value with minimal gelation when the polymerisable resin prepolymer is stored prior to be cured in the manufacture of a fibre-reinforced resin matrix composite material,
In this Example, the 2-Hydroxyethyl methacrylate was reacted with phthalic anhydride to form 2-hydroxyethyl methacrylate phthalate, otherwise called herein “Hema phthalate”. The reaction scheme is shown below:
Then the Hema phthalate and phthalic acid were reacted with liquid bisphenol-A epoxy resin to form a vinyl ester monomer, called herein “vinyl ester 7”. The general reaction scheme is shown below:
Hema phthalate was synthesized using the reaction scheme disclosed in Example 1 of WO-A-2011/073111. In order to synthesise the Hema phthalate, 2-hydroxyethyl methacrylate was added to a reactor having a top cover and which was sparged with a flow of air passing through the reactor. The 2-hydroxyethyl methacrylate was agitated and heated to at least 80° C. A catalytic amount of Triphenylphosphine (TPP) was added followed by a stoichiometric amount of phthalic anhydride. Following dissolution of all the phthalic anhydride, the reaction was allowed to continue until the viscosity levelled-off. The reaction period was between 4-10 hours. Phenothiazine (PTZ) was then added as an inhibitor, and was allowed to dissolve.
In order to synthesise the vinyl ester 7, the Hema phthalate was agitated and air sparged at all times throughout the subsequent synthesis. To the Hema phthalate, at a temperature of at least 80° C., a second amount of triphenylphosphine (TPP) was added followed by a liquid epoxy resin DER 330, and phthalic acid. The reaction was maintained at a temperature of at least 100° C. until the viscosity levelled-off. It was ensured that the viscosity had stabilised; determined as any change in viscosity over a 1 hour period being <5 Poise (as measured at 85° C. using a cone and plate method), before dispensing the vinyl ester prepolymer.
In order to form the curable resin film, the vinyl ester prepolymer was then mixed with the free-radical curing system. In this example, the free-radical curing comprised, for 100 parts by weight of the synthesised vinyl ester, 1.0 part by weight of tert-butyl peroxybenzoate (known under the brand name Luperox P) as a first peroxide curing agent, 0.6 parts by weight of part by weight of Nouryact CF12 as a first auxiliary curing agent and 0.4 parts by weight of 2,4-pentanedione as a second auxiliary curing agent.
The vinyl ester prepolymer was preheated to a temperature within the range of from 60 to 70° C. and the free-radical curing system was mixed into the vinyl ester prepolymer to achieve a homogeneous product, using a dual asymmetric centrifugal mixer. The auxiliary curing agents were added first and mixed in, and then the peroxide curing agents were added and mixed in.
Directly after mixing the vinyl ester prepolymer and the free-radical curing system, the homogeneous resin was formed into a resin film using a filming step. In the filming step, the resin was deposited onto a polyester scrim fabric having an areal weight of 15 gsm which was over a paper backing sheet. The desired film thickness was achieved using a heated knife over a roller.
The resultant vinyl ester 7 provided a polymerisable resin prepolymer for which the cold Tg (measured for the resin alone) and resin viscosity at 85° C. (measured for the combination of the resin and the curing system) were acceptable, as shown in
The resultant resin film comprising vinyl ester 7 resin and a curing system had the following properties, using the measurement methods described herein:
Rheology i.e. parameters that define the cure performance of the material, wet-out characteristics, stability on the roll and tack):
Reaction temperature and enthalpy, i.e. parameters that define storage stability at room temperature, cure performance and manufacturability:
| Number | Date | Country | Kind |
|---|---|---|---|
| 2111125.7 | Aug 2021 | GB | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2022/071743 | 8/2/2022 | WO |
