阅读说明：本技术 具有层间增韧颗粒的复合材料及其制造方法 (Composite material with interlaminar toughening particles and method for making same ) 是由 V·阿兹 W·雅各布斯 J·M·格里芬 于 2018-11-07 设计创作，主要内容包括：披露了一种纤维增强的聚合物复合结构,其具有位于相邻的增强纤维层之间的层间区域中的化学活性热固性颗粒,以及一种其制造方法。在固化该复合结构时,这些热固性颗粒上的化学活性官能团与这些颗粒周围的基质树脂形成共价键。在一个实施例中,这些颗粒由具有小于100％的固化度的部分固化的热固性聚合物形成。在另一个实施例中,这些颗粒衍生自可热固化树脂组合物,其中化学计量比是使得与100％的热固性树脂组分反应所需的固化剂的量存在不足或过量。在一些实施例中,这些化学活性热固性颗粒的组成与该复合结构的基质树脂的组成相同或基本上相同。(A fiber reinforced polymer composite structure having chemically active thermoset particles located in the interlaminar region between adjacent layers of reinforcing fibers, and a method of making the same, are disclosed. Upon curing the composite structure, the chemically active functional groups on the thermoset particles form covalent bonds with the matrix resin surrounding the particles. In one embodiment, the particles are formed from a partially cured thermoset polymer having a degree of cure of less than 100%. In another embodiment, the particles are derived from a thermally curable resin composition wherein the stoichiometric ratio is such that there is an insufficient or excessive amount of curing agent required to react with 100% of the thermosetting resin component. In some embodiments, the composition of the chemically active thermoset particles is the same or substantially the same as the composition of the matrix resin of the composite structure.)

1. A fiber reinforced polymer composite structure, comprising:

two or more layers of reinforcing fibres impregnated or infused with a curable matrix resin comprising one or more thermosetting resins and at least one curing agent;

chemically active thermoset particles located in the interlaminar regions between adjacent layers of reinforcing fibers,

wherein each chemically active thermoset particle is formed from a partially cured thermoset polymer having a degree of cure of less than 100%, preferably from 50% to 99%, and each particle comprises chemically active functional groups on its surface capable of forming covalent bonds.

2. The fiber reinforced polymer composite structure of claim 1, wherein the degree of cure of the partially cured thermoset polymer is 50% to 86%.

3. The fiber reinforced polymer composite structure of claim 1 or 2, wherein the chemically active thermoset particles are derived from a heat curable resin composition comprising one or more epoxy resins and at least one amine compound as a curing agent.

4. The fiber reinforced polymer composite structure of any of the preceding claims, wherein each chemically active thermoset particle comprises a crosslinked polyepoxide, uncrosslinked epoxy functional groups, and unreacted amine groups.

5. The fiber reinforced polymer composite structure of any of the preceding claims, wherein the composition of the chemically active thermoset particles is the same or substantially the same as the composition of the curable matrix resin.

6. The fiber reinforced polymer composite structure of any of the preceding claims, wherein the chemically active thermoset particles further comprise one or more additives selected from: a conductive material in particulate form, a thermoplastic polymer, an elastomer, and a flame retardant.

7. A fiber reinforced polymer composite structure, comprising:

two or more layers of reinforcing fibres impregnated or infused with a curable matrix resin comprising one or more thermosetting resins and at least one curing agent;

chemically active thermoset particles located in the interlaminar regions between adjacent layers of reinforcing fibers,

wherein each chemically active thermoset particle comprises a crosslinked thermoset polymer and a chemically active functional group capable of forming a covalent bond.

8. The fiber reinforced polymer composite structure of claim 7, wherein each chemically active thermoset particle comprises a crosslinked polyepoxide and an uncrosslinked epoxy functional group or an unreacted amine group.

9. The fiber reinforced polymer composite structure of claim 7 or 8, wherein the chemically active thermoset particles are derived from a heat curable resin composition comprising one or more epoxy resins and at least one amine compound as a curing agent, wherein the molar ratio of epoxy groups to amine groups is such that the amount of amine required to react with 100% of all epoxy groups is present in either an insufficient or an excessive amount.

10. A method of making a fiber reinforced polymer composite structure, the method comprising:

(a) forming thermosetting particles having chemically active functional groups on the surface of the particles;

(b) forming a plurality of prepreg plies, each prepreg ply comprising reinforcing fibers impregnated or infused with a curable matrix resin;

(c) depositing the partially cured thermosetting particles on at least one surface of each prepreg ply;

(d) laying up the prepreg plies having the particles thereon in a stacked arrangement such that the particles are located between adjacent prepreg plies, thereby forming a prepreg layup;

(e) consolidating the prepreg layup; and

(f) curing the prepreg layup;

wherein the thermosetting particles in (a) are formed by one of the following methods:

(i) partially curing a heat curable resin composition comprising one or more thermosetting resins and at least one curing agent to form a partially cured thermosetting resin having a degree of cure of less than 100%, preferably 50-99%; and grinding the partially cured thermosetting resin;

(ii) forming a heat-curable resin composition comprising one or more thermosetting resins and at least one curing agent, wherein the molar ratio of the one or more thermosetting resins to the curing agent is such that there is an insufficient or excessive amount of amine required to react with 100% of all epoxy resins; curing the heat-curable resin composition to form a crosslinked resin having chemically reactive functional groups; and grinding the crosslinked resin; and is

Wherein, during curing of (f), the chemically active functional groups on the thermoset particles form covalent bonds with the matrix resin surrounding the particles.

11. The method of claim 10, wherein the thermoset particles are produced by method (i) and the degree of cure of the partially cured resin is 50-86%.

12. A method of making a fiber reinforced polymer composite structure, the method comprising:

(a) forming thermosetting particles having chemically active functional groups on the surface of the particles;

(b) forming a curable matrix resin composition comprising one or more thermosetting resins, at least one curing agent, and the thermosetting particles;

(c) impregnating a plurality of layers of reinforcing fibers with the curable resin composition to form prepreg plies, each prepreg ply comprising reinforcing fibers impregnated or infused with the curable matrix resin composition and thermosetting particles retained at the outer surfaces of the layers of reinforcing fibers;

(d) laying up the plies of prepreg having particles therein in a stacked arrangement to form a prepreg layup;

(e) consolidating the prepreg layup; and

(f) curing the prepreg layup;

wherein the thermosetting particles in (a) are formed by one of the following methods:

(i) partially curing a heat curable resin composition comprising one or more thermosetting resins and at least one curing agent to form a partially cured thermosetting resin having a degree of cure of less than 100%, preferably 50-99%; and grinding the partially cured thermosetting resin;

(ii) forming a heat-curable resin composition comprising one or more thermosetting resins and at least one curing agent, wherein the molar ratio of the one or more thermosetting resins to the curing agent is such that there is an insufficient or excessive amount of amine required to react with 100% of all epoxy resin groups; curing the heat-curable resin composition to form a cured resin having chemically reactive functional groups; and grinding the cured resin; and is

Wherein, during curing of (f), the chemically active functional groups on the thermoset particles form covalent bonds with the matrix resin surrounding the particles.

13. A method of making a fiber reinforced polymer composite structure, the method comprising:

(a) forming thermosetting particles having chemically active functional groups on the surface of the particles;

(b) forming a resin film from a first curable resin composition that does not contain the thermosetting particles;

(c) forming a resin film from a second curable resin composition comprising one or more thermosetting resins, at least one curing agent, and the thermosetting particles;

(d) impregnating a layer of reinforcing fibers with at least one resin film formed from the first curable resin composition using heat and pressure, thereby forming a layer of resin-impregnated reinforcing fibers;

(e) contacting at least one resin film formed from the second curable resin composition with the surface of the resin impregnated reinforcing fiber layer, thereby forming a particle-containing prepreg ply;

(f) forming additional particle-containing prepreg plies according to steps (d) and (e);

(g) laying up the plies of prepreg in a stacked arrangement to form a prepreg layup;

(h) consolidating the prepreg layup; and

(i) curing the prepreg layup;

wherein the thermosetting particles in (a) are formed by one of the following methods:

(i) partially curing a heat curable resin composition comprising one or more thermosetting resins and at least one curing agent to form a partially cured thermosetting resin having a degree of cure of less than 100%, preferably 50-99%; and grinding the partially cured thermosetting resin;

(ii) forming a heat-curable resin composition comprising one or more thermosetting resins and at least one curing agent, wherein the molar ratio of the one or more thermosetting resins to the curing agent is such that there is an insufficient or excessive amount of amine required to react with 100% of all epoxy resins; curing the heat-curable resin composition to form a cured resin having chemically reactive functional groups; and grinding the cured resin; and is

Wherein, during curing of (i), the chemically active functional groups on the thermoset particles form covalent bonds with the matrix resin surrounding the particles.

14. The method of any one of claims 10 to 13, wherein the heat curable resin composition for forming the thermosetting particles comprises one or more epoxy resins and at least one amine compound as curing agent.

15. A method of making a fiber reinforced polymer composite structure, the method comprising:

(a) forming thermosetting particles having chemically active functional groups on the surface of the particles;

(b) forming a plurality of prepreg plies, each prepreg ply comprising reinforcing fibers impregnated or infused with a curable matrix resin;

(c) depositing the partially cured thermosetting particles on at least one surface of each prepreg ply;

(d) laying up the prepreg plies having the particles thereon in a stacked arrangement such that the particles are located between adjacent prepreg plies, thereby forming a prepreg layup;

(e) consolidating the prepreg layup; and

(f) curing the prepreg layup.

Drawings

Fig. 1 shows a Scanning Electron Microscope (SEM) image of milled thermoset particles prepared according to an example.

Figure 2 shows a cross-sectional view of the cured composite laminate in which the apparent interlaminar regions can be seen.

Detailed Description

Fiber Reinforced Polymer (FRP) composites have been used as high strength, low weight engineering materials to replace metals in aerospace structures, such as the primary structure of an aircraft. Important characteristics of such composite materials are high strength, high stiffness and reduced weight.

Multiple prepreg plies are commonly used to form structural composite parts having a laminated structure. Delamination of such composite parts is an important failure mode. Delamination occurs when two layers debond from each other. Important design constraints include both the energy required to initiate a delamination and the energy required to propagate a delamination.

Cured composites (e.g., prepreg layups) with improved delamination resistance are composites with improved post-impact compressive strength (CAI) and fracture toughness (G)_IcAnd G_IIc) The composite material of (1).

CAI measures the ability of a composite to resist damage. In the test to measure CAI, the composite material is subjected to an impact of a given energy and then loaded under compression. The damage area and the recess depth were measured after impact and before compression testing. During this test, the composite was constrained to ensure that no warpage instability occurred and the strength of the composite was recorded.

Fracture toughness is a property that describes the ability of materials containing cracks to resist fracture and is one of the most important properties of materials for aerospace applications. Fracture toughness is a quantitative way of expressing the resistance of a material to brittle fracture when a crack is present.

Fracture toughness can be quantified as strain energy release rate (G)_c) Which is the energy dissipated per unit of newly created fracture surface area during fracture. G_cComprising G_IC(mode 1-open mode) or G_IIC(mode II-in-plane shear). The subscript "IC" indicates that the mode I crack formed under normal tensile stress normal to the crack opens, and the subscript "IIC" indicates that the mode II crack results from shear stress acting parallel to the crack plane and normal to the crack front. Initiation and growth of delamination is typically determined by examining mode I and mode II fracture toughness.

The CAI properties of fiber reinforced polymer composites can be improved by two main techniques. The first technique involves the use of high strength reinforcing fibers, which have a relatively high strain to failure. These fibers appear to absorb a large amount of energy without breaking, thereby redistributing the energy over a larger area of the composite laminate.

CAI Properties and interlaminar toughness (G) of fiber-reinforced Polymer composites_ICAnd G_IIC) Certain toughening may be incorporated in the interlaminar region of a multilayer composite laminate byAnd (3) particle improvement. "interlaminar region" refers to the region between two adjacent layers of reinforcing fiber structure in a composite laminate. The presence of the toughening particles in the composite laminate creates a resin rich interlayer which helps to inhibit crack propagation in this interlayer region.

Conventionally, thermoplastic particles, such as Polyamide (PA), have been incorporated into the interlaminar regions of composite laminates to improve CAI. "interlaminar region" refers to the region between adjacent layers of reinforcing fibers in a multilayer composite laminate. However, thermoplastic particles based on polyamides may have a low melting point (Tm), especially those with long aliphatic chains, or have an excessively high hygroscopicity, such as those with short aliphatic chains. Amorphous thermoplastic particles (such as amorphous PA or PI) may have poor solvent resistance. Another commonly encountered problem is the creation of poor interfaces between the thermoplastic particles and the thermoset matrix in which they are embedded, due to Coefficient of Thermal Expansion (CTE) mismatches between the particles and the surrounding resin matrix. This mismatch in CTE can lead to debonding during thermal cycling testing. This is commonly referred to as microcracking and is a major problem in the aerospace industry.

The present disclosure relates to the use of chemically active or "active" thermoset particles as interlaminar toughening particles for improving damage tolerance and fracture toughness of fiber reinforced polymer composites. More specifically, the particles contain chemical functional groups that can react with the thermally curable resin matrix, the chemical functional groups being dispersed in the thermally curable resin matrix to form covalent bonds during curing of the resin matrix.

In one embodiment, the chemically active particle is obtained by: the heat curable resin composition is partially cured beyond its gel point to achieve a "solid-like" character, followed by grinding to achieve the desired particle size. Unreacted or uncrosslinked functional groups are present on the particle surface due to partial curing. The particles are sufficiently cross-linked beyond the gel point of the resin composition to maintain particle integrity and ensure the formation of significant interlaminar regions when curing the composite laminate in which the particles are embedded.

In another embodiment, the heat curable resin composition is formulated such that the ratio of the one or more thermosetting resins to the one or more curing agents in the curable resin composition is adjusted such that the composition contains a non-stoichiometric ratio of the one or more thermosetting resins and the one or more curing agents, i.e., the amount of the one or more curing agents required to react with 100% of the one or more thermosetting resins is insufficient or excessive, and thus, at the end of the entire curing cycle, unreacted or uncrosslinked functional groups from the thermosetting resin or curing agent will be present due to this insufficiency or excess. After complete curing, the cured resin is then milled to obtain particles having chemically active functional groups on the surface of the particles. In this example, the resulting chemically active thermoset particles are comprised of a crosslinked thermoset resin or thermoset polymer and chemically active functional groups capable of forming covalent bonds. When the particles are formed from a heat curable resin composition containing one or more epoxy resins, the resulting chemically active thermoset particles are comprised of a crosslinked polyepoxide and uncrosslinked functional groups.

The partially cured particles may be formed from the same or substantially the same curable resin composition used to form the matrix resin of the fibre-reinforced composite material (e.g. prepreg). The term "substantially the same" means that greater than 50% of the compositions are the same. In one embodiment, some of the matrix resin used to form the composite material may be set aside for partial curing and grinding to form the chemically active particulates. The partially cured particles are then incorporated into the composite laminate at the interlaminar regions. In this way, the CTE of the particles will be precisely matched to the CTE of the surrounding resin matrix, thereby eliminating stress and microcracks in the cured composite laminate. In addition, since the particles are made of the same or similar material as the matrix resin, the interfacial bonding between the particles and the surrounding matrix resin is strong after curing.

It has been found that little or no CTE mismatch occurs between the "active" (chemically active) thermoset particles and the surrounding resin matrix, and thus the cured composite laminate exhibits improved debond and microcrack resistance. As disclosed herein, the use of "active" thermoset particles is different from conventional methods used in the aerospace industry, where thermoplastic or crosslinked thermoplastic toughening particles having different chemistry from the surrounding matrix resin are used as interlayer toughening particles.

The "active" thermoset particles disclosed herein are non-swellable during curing, as in the case of the crosslinked thermoplastic particles disclosed in U.S. patent No. 8,846,818 and U.S. patent No. 9,567,426. The swellable crosslinked thermoplastic particles disclosed in these patents are crosslinked, derived from compositions consisting essentially of thermoplastic polymers, and typically do not retain reactive functional groups on the surface of the particles. Likewise, the swellable particles are not very reactive with the surrounding epoxy-based matrix of the composite material in which they are dispersed.

Chemically active thermoset particles

As used herein, the terms "cure" and "curing" include crosslinking of a resin precursor or polymer by mixing the base components, heating at elevated temperatures, exposure to ultraviolet light and radiation. As used herein, "fully cured" refers to a degree of cure of 100%. As used herein, "partially cured" refers to a degree of cure of less than 100%.

The partially cured particles are formed from a curable resin composition that has been cured to a degree of cure of less than 100%, for example in the range of 50-99%, including 55-95%, 50-86%, 50-87%, 50-88%, 50-89%, 55-86%, 60-86% of full cure. The curable resin composition contains one or more thermosetting resins, at least one curing agent, and optional additives such as thermoplastic polymers, elastomeric materials, conductive microparticles, organic fillers, and the like. At a degree of cure of 50% or more, the thermomechanical properties of the material change significantly and the material has "solid-like" properties.

In order to form partially cured particles, thermal curing is performed beyond the gel point of the resin composition. This gel point may be defined as the intersection between the G' and G "curves derived from the rheological analysis during the cure cycle. G' represents the elastic modulus, and G "represents the viscous modulus.

The degree of cure of the thermosetting resin system can be determined by Differential Scanning Calorimetry (DSC). Thermosetting resin systems undergo irreversible chemical reactions during curing. When the components of the resin system cure, the resin releases heat, which is monitored by the DSC instrument. The curing heat may be used to determine the percent cure of the resin material. For example, the following simple calculations may provide this information:

% cure ═ Δ H_Uncured-ΔH_Cured]/[ΔH_Uncured]X 100％

By way of example, when the particles are formed from a heat curable resin composition containing one or more epoxy resins and an amine compound as a curing agent, the resulting chemically active thermoset particles are comprised of a crosslinked polyepoxide, uncrosslinked epoxy functional groups, and unreacted amine groups.

In an alternative embodiment, the ratio of the one or more thermosetting resins to the one or more curing agents in the curable resin composition is adjusted such that the composition contains an insufficient or excessive amount of the one or more curing agents required to react with 100% of the one or more thermosetting resins, and therefore, at the end of the predetermined curing cycle, unreacted or uncrosslinked functional groups from the thermosetting resin material will be present due to this insufficient or excessive amount. For example, if an amount of X curing agent is required to achieve 100% cure in a predetermined cure cycle, less than X amount of curing agent may be used in the resin composition to achieve chemically active particles, such as up to 90% X, including 50% -80% X, or 60% -70%. Alternatively, if an amount of X curing agent is required to achieve 100% cure in a predetermined cure cycle, an amount greater than X may be used in the resin composition to obtain chemically active particles, for example at least 110% X, including 120% -150% X or 130% -140%.

To determine the lowest possible amount of curing agent (i.e., hardener) within a useful range, the simplified Carothers equation described in robert j.young, article a.lovell, Introduction to Polymers [ polymer theory ], Third Edition ], pages 46-47 (CRC press, 2011, 6/27 th) may be employed. For a given epoxy resin or other thermosetting resin having a functionality (e.g., 2, 3,4, etc.), the simplified carrousel equation is a method of predicting the amount of conversion (degree of reaction) required to reach the gel point when reacted with a curing agent having a given functionality (e.g., 2, 3,4, etc.). The relationship between gel point and available functionality for crosslinking is defined as n-2/2-pf, where n-the number average degree of polymerization, p-the decimal range of reaction, where 1 represents 100% reaction, and f-the total number of functional groups that undergo crosslinking reaction. This equation typically defines the gel point when n is infinite. For trifunctional epoxy resins and difunctional hardeners, the total functionality is 5 when p is 0.4 or 40% conversion, so n is infinite. For tetra-functional epoxy resins and tetra-functional hardeners (e.g., diprimary amines), f ═ 8 and gels, etc. are predicted to occur at 25% conversion.

Upon complete curing of the resin composition, the cured material contains unreacted/uncrosslinked functional groups that are a source of chemically active functional groups capable of forming covalent bonds. For example, when an epoxy resin and an amine curing agent are used and an amine compound is present insufficiently, the resulting cured particles contain unreacted/uncrosslinked epoxy functional groups. Conversely, when the amine compound is present in excess, the resulting cured particles contain unreacted amine groups.

As an example, when the particles are formed of a heat-curable resin composition containing one or more epoxy resins and an amine compound as a curing agent, and when the amine compound is insufficient, the resulting chemically active thermosetting particles are composed of a crosslinked polyepoxide and an uncrosslinked epoxy functional group due to an excess of one or more epoxy resins.

The chemically active particulates may have an average particle size (d50) of less than about 100 μm, for example 10-70 μm, 15-50 μm or 15-30 μm or 20-25 μm. As disclosed herein, the average particle size can be measured by laser diffraction techniques, for example using a Malvern Mastersizer 2000 operating in the range of 0.002 nanometers to 2000 microns. "d 50" represents the median value of the particle size distribution, or alternatively a distribution value such that 50% of the particles have a particle size of that value or less.

Suitable thermosetting resins for forming the particles include, but are not limited to, epoxy resins, phenolic resins, phenols, cyanate esters, bismaleimides, benzoxazines, polybenzoxazines, combinations thereof, and precursors thereof.

Particularly suitable are multifunctional epoxy resins (or polyepoxides) having multiple epoxide functional groups per molecule. The polyepoxide may be a saturated, unsaturated, cyclic, or acyclic, aliphatic, aromatic, or heterocyclic polyepoxide compound. Examples of suitable polyepoxides include the polyglycidyl ethers prepared by the reaction of epichlorohydrin or epibromohydrin with a polyphenol in the presence of a base. Suitable polyphenols are therefore, for example, resorcinol, catechol, hydroquinone, bisphenol A (bis (4-hydroxyphenyl) -2, 2-propane), bisphenol F (bis (4-hydroxyphenyl) -methane), fluoro 4,4 '-dihydroxybenzophenone, bisphenol Z (4, 4' -cyclohexylidene-bisphenol) and 1, 5-hydroxynaphthalene. Other suitable polyphenols as the basis for the polyglycidyl ethers are the known condensation products of phenol and formaldehyde or acetaldehyde of the novolac resin type.

Examples of suitable epoxy resins include diglycidyl ethers of bisphenol A or bisphenol F, such as EPON available from Dow Chemical Co^TM828 (liquid epoxy), d.e.r.331, d.e.r.661 (solid epoxy); triglycidyl ethers of aminophenols, e.g. from Hensman CorpMY0510, MY 0500, MY 0600 and MY 0610. Additional examples include phenol-based novolac epoxy resins, commercially available from the dow chemical company as DEN428, DEN 431, DEN 438, DEN 439, and DEN 485; cresol-based novolac epoxy resins commercially available from Ciba-Geigy Corp as ECN 1235, ECN 1273, and ECN 1299; hydrocarbon novolac epoxy resins from Hensman as71756、556. And756 are commercially available.

The curing agent for the curable resin composition may be selected from known curing agents, such as aromatic or aliphatic amines or guanidine derivatives. Aromatic amine curing agents are preferred, aromatic amines having at least two amino groups per molecule are preferred, and diaminodiphenyl sulfone is particularly preferred, for example, where the amino groups are meta or para with respect to the sulfone groups. Specific examples are 3,3 '-and 4,4' -diaminodiphenyl sulfone (DDS); methylenedianiline; bis (4-amino-3, 5-dimethylphenyl) -1, 4-diisopropylbenzene; bis (4-aminophenyl) -1, 4-diisopropylbenzene; 4,4' methylenebis- (2, 6-diethyl) -aniline (MDEA from the desazaar group (Lonza)); 4,4' methylenebis- (3-chloro, 2, 6-diethyl) -aniline (MCDEA from the dragon sand group); 4,4' methylenebis- (2, 6-diisopropyl) -aniline (M-DIPA from the dragon sand group); 3, 5-diethyltoluene-2, 4/2, 6-diamine (D-ETDA 80 from the Dragon Sand group); 4,4' methylenebis- (2-isopropyl-6-methyl) -aniline (M-MIPA from the losa group); 4-chlorophenyl-N, N-dimethyl-urea (e.g., Monuron); 3, 4-dichlorophenyl-N, N-dimethyl-urea (e.g., DiuronTM) and dicyanodiamide (e.g., Amicure TMCG 1200 from Pacific Anchor Chemical).

Suitable curing agents also include anhydrides, particularly polycarboxylic anhydrides such as nadic anhydride, methylnadic anhydride, phthalic anhydride, tetrahydrophthalic anhydride, hexahydrophthalic anhydride, methyltetrahydrophthalic anhydride, endomethylenetetrahydrophthalic anhydride, and trimellitic anhydride.

To form partially cured particles, the one or more curing agents may be present in a stoichiometric amount such that there is a sufficient amount of reactive groups from the curing agent to react with the reactive groups of the one or more thermosetting resins, e.g., one (1) mole of amine curing agent per mole of epoxy resin. To form fully cured but chemically reactive particles, the stoichiometry is such that there is an insufficient amount of reactive groups from the curing agent to react with the reactive groups of the thermosetting resin or resins, for example 0.5 to 0.9 moles of amine curing agent per mole of epoxy resin. Alternatively, to form a fully cured but chemically reactive particle, the stoichiometry is such that there is an excess of reactive groups from the curing agent to react with the reactive groups of the thermosetting resin or resins, e.g., 1.1 to 1.5 moles of amine curing agent per mole of epoxy resin.

Optional additives that may be incorporated into the curable resin composition include thermoplastic polymers, elastomers, and combinations thereof. The thermoplastic polymer may be selected from: a polyamide; polyetherimide (PEI); polysulfones, including polyether sulfone (PES), polyether ether sulfone (PEES); polyphenylene Oxide (PPO); poly (ethylene oxide) (PEO), phenoxy resins (thermoplastic copolymers of bisphenol a and epichlorohydrin), Polyimides (PI), Polyamideimides (PAI), polysulfones (Psu) … copolymers and combinations thereof. The elastomer may be selected from: rubbers such as amine-terminated butadiene Acrylonitrile (ATBN), carboxyl-terminated butadiene acrylonitrile (CTBN), carboxyl-terminated butadiene (CTB); fluorocarbon elastomers, styrene-butadiene polymers. When present, the amount of thermoplastic polymer and/or elastomer is less than 40%, for example, 5% to 35% by weight of thermoplastic polymer based on the total weight of the resin composition, so that the particles retain their thermoset character.

Conductive materials in particulate form (e.g., granules or flakes) may also be added to the curable resin composition to impart electrical conductivity, also referred to as Z-conductivity, throughout the thickness of the final composite laminate. Examples of suitable conductive materials include metals in the form of flakes or particles, such as silver, gold, nickel, copper, aluminum, and alloys thereof, carbon powder, carbon-based nanosized materials, such as carbon nanotubes (single-walled or multi-walled carbon nanotubes), carbon nanofibers. As used herein, the term "nano-sized material" refers to a material having at least one dimension that is less than about 0.1 micron (<100 nanometers). Carbon Nanotubes (CNTs) are tubular, strand-like structures having an outer diameter in the range of about 0.4nm to about 100nm (e.g., the outer diameter can be less than about 50nm or less than about 25nm) and an aspect ratio of from 100:1 up to 5000: 1. The nanofibers may have a diameter in the range of from 70nm to 200nm and a length in the range of 50-200 microns. When present, the amount of conductive material is less than 10% by weight, for example, 1% to 4% by weight, based on the total weight of the resin composition.

Flame retardant additives may also be added to the curable resin composition to impart enhanced added flame retardancy to the final composite laminate. For example, the Strujtol Polydis product line, commercialized by the Hilen Selch company (Schill + Seilacher). Other commercially available flame retardants will be apparent to those skilled in the art.

In one embodiment, the particles are formed from a curable resin composition comprising: (a) one or more multifunctional epoxy resins; (b) at least one amine curing agent; and (c) a thermoplastic or elastomeric toughener. The amounts of components (a) - (c) may be as follows: (a)100 parts of (A); (b)5 to 70 parts; (c)5 to 50 portions.

In another embodiment, the resin composition further includes conductive particles, such as Carbon Nanotubes (CNTs), carbon powder, metal particles, and combinations thereof. When present, the amount of conductive particles is up to 10% by weight, e.g., 1% to 10%, 2% to 5%, based on the total weight of the resin composition.

It will be understood by those skilled in the art that the chemically active thermoset particles of the present disclosure may be formed by other methods capable of producing such particles, rather than partial curing followed by grinding.

Composite material and laminate

The chemically active particles of the present disclosure may be used as interlaminar particles between layers of reinforcing fibers of a composite laminate, i.e., the particles are located in the interlaminar region of the composite laminate. "interlaminar region" refers to the region between adjacent layers of reinforcing fibers in a multilayer composite laminate.

In some embodiments, the chemically active particulates are dispersed in the interlaminar region formed between adjacent layers of reinforcing fibers at a level of from about 2% to about 20%, including from about 5% to about 15%, and from about 8% to about 12% by weight based on the total weight of the matrix resin contained in the composite laminate.

Composite laminates containing interlaminar particles can be made using different methods. In one embodiment, the particles are deposited on the surface of the prepreg plies before the plurality of prepreg plies are laid together to form a stack or "prepreg layup". The prepreg plies within the laminate may be positioned in a selected orientation relative to each other, e.g., 0 °, ± 45 °, 90 °, etc. When the prepreg plies are stacked together to form a laminate, the particles remain in the interlaminar regions of the laminate. Once in place, the prepreg layup is consolidated and cured under heat and pressure to achieve the desired fiber volume fraction and minimum voids.

These particles may be deposited onto the prepreg via any conventional technique such as spraying, electrostatic deposition, scatter coating, spray distribution, and any other technique known to those skilled in the art. Due to the viscosity of the matrix resin, the distributed composite particles adhere to the surface of the prepreg.

In another embodiment, a specific amount of particles is mixed with a curable resin composition prior to the prepreg manufacture. In such an embodiment, a resin film is first manufactured by coating a particle-containing resin mixture onto a release paper. The resulting resin film is then laminated to a layer of fibers (e.g., unidirectional fibers) with the aid of heat and pressure to impregnate the fibers, thereby forming a prepreg ply having a specific fiber areal weight and resin content. During the impregnation process, the particles are filtered out and remain outside the fibre layer, since the size of the particles is larger than the spacing between the fibres. Subsequently, when two prepreg layers containing particles are laid on top of each other, these particles are located in the interlaminar region of the prepreg layup.

In an alternative embodiment, the curable resin composition without particles is coated onto a release paper to form a resin film, which is then contacted with one or both opposing surfaces of the unimpregnated fiber layer. The resin impregnates the fibers and leaves little or no resin on the outer surface of the fiber layer. Subsequently, a second film of curable resin containing particles is brought into contact with the outer surface of the resin impregnated fibrous layer. An additional film of curable resin containing particles may be brought into contact with the opposite outer surface of the resin impregnated fibrous layer to form a sandwich structure. As a result, the particle-rich resin layer remains outside the impregnated fiber layer and does not further impregnate the fibers. A plurality of such structures are laminated together to form a composite structure having particles in the interlayer region.

In another embodiment, two films of the curable resin composition without particles are brought into contact with two opposite surfaces of the unimpregnated fibre layer. The resin impregnates the fibers and leaves little or no resin on the outer surface of the fiber layer. Subsequently, two films of curable resin containing particles are brought into contact with opposite surfaces of the pre-impregnated fibre plies. A plurality of such structures are laminated together to form a composite structure having particles in the interlayer region. This approach is preferred because it tends to provide a well-ordered laminate produced from the particles without disrupting the placement of the fibers.

In embodiments disclosed herein, the term "prepreg" refers to a layer of fibrous material (in the form of unidirectional fibers, a non-woven mat, or a fabric layer) that has been impregnated or infused with a curable matrix resin. As used in this disclosure, the term "impregnation" refers to the introduction of a curable resin into the reinforcing fibers so as to partially or fully encapsulate the fibers with the matrix resin.

The matrix resin of the prepreg may have a composition that is the same as or similar to the composition of the chemically active particles. Likewise, the thermosetting resins, curing agents and additives previously disclosed with respect to the particles are also applicable to the matrix resin of the prepreg.

The fibrous reinforcement may be in the form of woven or nonwoven fabric layers, or unidirectional tapes composed of unidirectional fibers. "unidirectional fibers" refers to layers of reinforcing fibers aligned in the same direction. The prepreg plies within the laminate may be positioned in a selected orientation relative to each other, e.g., 0 °, ± 45 °, 90 °, etc.

The reinforcing fibers in the composite laminates and prepregs may take the form of chopped fibers, continuous fibers, filaments, tows, bundles, sheets, plies, and combinations thereof. The continuous fibers may further take any of unidirectional (aligned in one direction), multidirectional (aligned in a different direction), non-woven, knitted, stitched, wound, and braided configurations, as well as structures of crimped fiber mats, felt mats, and chopped mats. The woven fibrous structure may comprise a plurality of woven tows, each tow being composed of a plurality of filaments (e.g., thousands of filaments). In other embodiments, the tows may be held in place by cross-tow stitching, weft knit stitching, or a small amount of a resin binder (e.g., a thermoplastic resin).

Fibrous materials include, but are not limited to, glass (including electro-or E-glass), carbon, graphite, aramid, polyamide, high modulus Polyethylene (PE), polyester, poly-p-phenylene-benzoxazole (PBO), boron, quartz, basalt, ceramic, and combinations thereof.

For the manufacture of high strength composites, such as those used in aerospace and automotive applications, it is preferred that the reinforcing fibers have a tensile strength greater than 3500MPa (according to ASTM D4018 test method).

Examples of the invention

Example 1

Resin system U without toughening particles ("resin U") was prepared based on the formulation shown in table 1.

TABLE 1

Components	Unit of	Resin U
			Araldite MY0510	By weight%	27.6
Araldite PY306	By weight%	27.6
			Aradur 9664-1	By weight%	27.3
Sumikaexcel 5003P	By weight%	17.5

By oxidizing an epoxy precursorAndPY306 is mixed at a temperature ranging between 60 ℃ and 90 ℃ to prepare resin U.MY0510 is triglycidyl-p-aminophenol, andPY306 is a diglycidyl ether of bisphenol-F, both from Huntsman advanced Materials Inc. Sumikaexcel 5003P (polyethersulfone from sumitomo chemical) was added to the epoxy mixture and then dissolved at a temperature ranging between 110 ℃ and 130 ℃. Then adding aromatic amine curing agent9664-1(4, 4' -diaminodiphenyl sulfone from Hensmei advanced materials Co., Ltd.) (4, 4-DDS)) and mixed at a temperature ranging between 60 ℃ and 90 ℃.

The resin U so produced was then filmed on release paper to a nominal areal weight of 23.4gsm (grams per square meter). The medium modulus carbon fibers were spread in a conventional prepreg machine to form a web of unidirectional fibers having a nominal areal weight of 190 gsm. The formed web was then sandwiched between two films of resin U to obtain prepreg U having a nominal Fiber Area Weight (FAW) of 190gsm and a nominal resin content of 19.8% by weight.

Four resin compositions, P.1-P.4, were prepared based on the formulations shown in Table 2, one without particles and three with different reactive thermoset toughening particles. All amounts are in weight%.

TABLE 2

By oxidizing an epoxy precursorMY0510 andPY306 is mixed at a temperature ranging between 60 ℃ and 90 ℃ to prepare each of the resin compositions in table 2. Sumikaexcel 5003P (polyethersulfone) was added and then dissolved at a temperature ranging between 110 ℃ and 130 ℃. Then adding9664-1(4, 4' -DDS) and active thermosetting resin particles (LRTP), and mixed at a temperature ranging between 60 ℃ and 90 ℃.

Each resin composition P thus produced was then film-formed onto a release paper to a nominal areal weight of 23.4 gsm. The prepreg U formed as described above was sandwiched between two resin films formed from the particle-containing resin composition P using a conventional prepreg machine to obtain a prepreg P having a nominal Fiber Areal Weight (FAW) of 190gsm and a total nominal resin content of 33% by weight.

The different toughening particles used are labelled VP-0X0, PK-0X0, NT-0X0 in Table 2. The three toughening particles were prepared using the resin formulations shown in table 3.

TABLE 3

By reacting the epoxy precursors Tactix123 andPY306 is mixed at a temperature ranging between 60 ℃ and 90 ℃ to prepare resins VP-0X0, PK-0X0, NT-0X 0. Tactix123 is the diglycidyl ether of bisphenol A from Hensmei advanced materials.

VP-0X0 resin: VP3619 and9664-1, and mixing at a temperature ranging between 70 ℃ and 90 ℃. Struktol VP3619 is a nitrile rubber modified epoxy prepolymer based on the diglycidyl ether of bisphenol a from scherrer company.

PK-0X0 resin: PKHB100 (a polyhydroxyether (i.e., phenoxy resin) from the inc. of ichem) was added to the epoxy mixture and then dissolved at a temperature ranging between 110 ℃ and 130 ℃. The aromatic amine curing agent, Aradur 9664-1(4, 4' -DDS), was then added and mixed at a temperature ranging between 60 ℃ and 90 ℃.

NT-0X0 resin: the multi-walled carbon nanotubes were pre-dispersed in a Tactix123/PY306 blend. The aromatic amine curing agent, Aradur 9664-1(4, 4' -DDS), was then added and mixed at a temperature ranging between 60 ℃ and 90 ℃.

Three different particles (VP-0X0, PK-0X0, NT-0X0) were prepared by: the three resins VP-0X0, PK-0X0, NT-0X0 were partially cured by heating to 180℃ at 2 deg.C/min and cooling them immediately after reaching 180 deg.C. The resulting partially cured resin was pelletized prior to grinding with an ACM classified grinder from leptochaete corporation (Hosokawa). Differential Scanning Calorimetry (DSC) tests were performed on the initial three resins VP-0X0, PK-0X0, NT-0X0, and the three particles VP-0X0, PK-0X0, NT-0X0 made as described above, and the percent conversion of each of the three particles was determined using the following equation:

% cure ═ Δ H_Uncured-ΔH_Cured]/[ΔH_Uncured]X 100％。

Glass transition temperatures (T) of the three particles_g) Also obtained from these DSC tests. Finally, the particle size distribution of these particles was measured by laser diffraction using a Mastersizer 3000 from Malvern (Malvern). The results are summarized in table 4.

TABLE 4

Fig. 1 is a Scanning Electron Microscope (SEM) image of abrasive particles PK-0X0 disclosed in table 4.

A plurality of prepregs P are laid up to form a composite laminate. The laminate was closed in a conventional zero bleed sealed vacuum bag and cured in an autoclave at 85psi (586kPa or kPa) at 180 ℃ for 2 hours while maintaining the vacuum throughout the cure cycle.

The cured panels were then subjected to a damage resistance test (CSAI) and a microcrack test. The results are reported in table 5.

TABLE 5

	Resin P.1	Resin P.2	Resin P.3	Resin P.4
					CSAI[ksi]	26	38.7	39.1	34.8
CSAI[MPa]	179	267	269.6	240
					Micro-cracking of particles	Not applicable to	0	0	0

The results presented in table 5 demonstrate the benefit of incorporating these active thermosetting toughening particles to improve impact performance up to 50% without causing any particle microcracking problems.

Figure 2 shows a cross-section of the cured composite laminate in which the apparent interlaminar regions can be seen.

After 1,200 thermal cycles between-55 ℃ and 70 ℃, the heat-resistant micro-peeling was evaluated by microscopy. No microcracks were found after this test.