Patent Application
20150328848
Synthetic composite materials possess desirably high strength-to-weight ratios; however, composites typically lack dynamic functionality that occurs in natural composite materials. Natural composite materials, for example, rely on pervasive vascular networks to enable a variety of biological functions, in both soft and hard tissue. Composite structures such as bone tissue or wood are lightweight and have high strength, yet contain extensive vasculature capable of transporting mass and energy.
An ongoing challenge in materials science is the development of microvascular networks in synthetic composites, where the composite materials may be formed using conventional composite manufacturing processes. Specialized fabrication methods such as laser-micromachining, soft lithography, templating with degradable sugar fibers, and incorporating hollow glass or polymeric fibers can produce some microvascular structures in composite materials These specialized methods, however, are not currently suitable for rapid, large-scale production of fiber-reinforced composites with complex vasculatures.
In one approach to microfluidic composites, relatively short microfluidic channels are provided in a matrix in the form of hollow glass fibers (WO 2007/005657 to Dry). The glass fibers are present as repair conduits containing a fluid that can heal a crack in the composite matrix. A significant limitation of this approach is the brittle nature of the hollow glass fibers, which limits the shapes and lengths of microfluidic channels that can be present in the composite. In addition, the glass fibers cannot readily be used to form a microfluidic network.
In another approach to microfluidic composites, microfluidic channels are formed in a polymeric matrix by arranging hollow polymeric fibers and then forming the matrix around the hollow polymeric fibers (U.S. Publication No. 2008/0003433 to Mikami). Hollow polymeric fibers may offer a wider variety of microfluidic channel shapes than those available from hollow glass fibers. This approach, however, also has a number of limitations, including an inability to form a network from the individual hollow fibers, the relatively small number of materials available as hollow fibers, and the possibility of incompatibility between the hollow fiber and the matrix and/or between the hollow fiber and substances introduced into the channels.
Microfluidic networks can be formed in a polymeric matrix using a three-dimensional (3-D) direct-write assembly technique (U.S. Publication No. 2008/0305343 to Toohey et al.). While this fabrication method provides excellent spatial control, the resulting networks typically will not survive the mechanical and/or thermal stresses encountered in the conventional processes of forming reinforced composites.
It is desirable to provide microvascular networks in synthetic composites, where the composite materials may be formed using conventional composite manufacturing processes. It is desirable for the microfluidic channels of the networks to be available in a variety of shapes and dimensions. It also is desirable for a variety of polymeric materials to be available as the polymeric matrix of such a composite.
In one aspect, the invention provides a microvascular system that includes a solid polymeric matrix and a woven structure in the matrix. The woven structure includes a plurality of fibers, and a plurality of microfluidic channels, where at least a portion of the microfluidic channels are interconnected.
In another aspect of the invention, there is a method of making a microvascular system including forming a composite that includes a solid polymeric matrix and a plurality of sacrificial fibers in the matrix, heating the composite to a temperature of from 100 to 250° C., maintaining the composite at a temperature of from 100 to 250° C. for a time sufficient to form degradants from the sacrificial fibers, and removing the degradants from the composite to provide a network of microfluidic channels. The degradants have an average molecular weight less than 500 Daltons.
In another aspect of the invention, there is a method of making a microvascular system including forming a composite that includes a solid polymeric matrix and a woven structure in the matrix, heating the composite to a temperature of from 100 to 250° C., maintaining the composite at a temperature of from 100 to 250° C. for a time sufficient to form degradants from the sacrificial fibers, and removing the degradants from the composite to provide a plurality of microfluidic channels. The woven structure includes a plurality of fibers and a plurality of sacrificial fibers. The degradants have an average molecular weight less than 500 Daltons.
In another aspect of the invention, there is a thermally degradable polymeric fiber that includes a polymeric fiber matrix including a poly(hydroxyalkanoate) and a metal selected from the group consisting of an alkali earth metal and a transition metal, in the fiber matrix. The concentration of the metal in the fiber matrix is at least 0.1 wt %.
In another aspect of the invention, there is a method of making a degradable polymeric fiber including combining a fiber that includes a poly(hydroxyalkanoate) and a composition that includes a fluorinated fluid and a metal selected from the group consisting of an alkali earth metal and a transition metal. The method further includes maintaining the fiber and the composition together at a temperature and for a time sufficient to provide a concentration of the metal in the fiber of at least 0.1 wt %, and separating the fiber and the fluorinated fluid.
In another aspect of the invention, there is a method of making a degradable polymeric fiber including forming a spinning liquid that includes a poly(hydroxyalkanoate), a solvent, and a metal selected from the group consisting of an alkali earth metal and a transition metal. The method further includes passing the spinning liquid through a spinneret to form a fiber containing the poly(hydroxyalkanoate) and the metal; and drying the fiber to provide a concentration of the metal in the fiber of at least 0.1 wt %.
In another aspect of the invention, there is a self-healing composite system that includes a solid polymeric matrix and a woven structure in the matrix. The woven structure includes a plurality of fibers, and a first plurality of microfluidic channels. The microfluidic channels include a first healing agent in the channels.
In another aspect of the invention, there is a self-healing composite system that includes a solid epoxy matrix, and a woven structure in the matrix. The woven structure includes a plurality of fibers, a first plurality of microfluidic channels having an average diameter of from 20 to 500 micrometers, and a second plurality of microfluidic channels having an average diameter of from 20 to 500 micrometers. The first plurality of microfluidic channels includes a first part of an epoxy polymerizer in the channels, and the second plurality of microfluidic channels includes a second part of the epoxy polymerizer in the channels.
In another aspect of the invention, there is a method of making a self-healing composite system that includes forming a composite including a solid polymeric matrix, and a plurality of sacrificial fibers in the matrix; heating the composite to a temperature of from 100 to 250° C.; maintaining the composite at a temperature of from 100 to 250° C. for a time sufficient to form degradants from the sacrificial fibers, the degradants having an average molecular weight less than 500 Daltons; removing the degradants from the composite to provide a network of microfluidic channels; and introducing a healing agent into the network of microfluidic channels.
To provide a clear and more consistent understanding of the specification and claims of this application, the following definitions are provided.
The term “polymeric” means a substance that includes a polymer.
The term “polymer” means a substance containing more than 100 repeat units. The term “polymer” includes soluble and/or fusible molecules having long chains of repeat units, and also includes insoluble and infusible networks. The term “prepolymer” means a substance containing less than 100 repeat units and that can undergo further reaction to form a polymer.
The term “matrix” means a continuous phase in a material.
The term “matrix precursor” means a composition that will form a polymer matrix when it is solidified. A matrix precursor may include a monomer and/or prepolymer that can polymerize to form a solid polymer matrix. A matrix precursor may include a polymer that is dissolved or dispersed in a solvent, and that can form a solid polymer matrix when the solvent is removed. A matrix precursor may include a polymer at a temperature above its melt temperature, and that can form a solid polymer matrix when cooled to a temperature below its melt temperature.
The term “woven structure” means a single ply of an assembly of threads, where the threads are oriented in at least 2 directions within the ply.
The term “microfluidic channel” means a substantially tubular structure having a diameter less than 1,000 micrometers.
The term “microfluidic network” means a plurality of channels having a plurality of interconnects, where at least a portion the channels have a dimension less than 1,000 micrometers.
The term “fluid communication” means that two objects are in an orientation, and within a sufficient proximity to each other, such that fluid can flow from one object to the other. The term “fluid” means a substance in the liquid or gaseous state. In one example, if a microfluidic channel embedded in a matrix is in fluid communication with a surface of the matrix, then fluid can flow from the channel onto the surface.
The term “healing agent” means a substance that can contribute to the restoration of structural integrity to an area of a material that has been subjected to damage. Examples of healing agents include polymerizers, activators for polymerizers, solvents, and mixtures of these.
The term “polymerizer” means a composition that will form a polymer when it comes into contact with a corresponding activator for the polymerizer. Examples of polymerizers include monomers of polymers, such as styrene, ethylene, acrylates, methacrylates, and cyclic olefins such as dicyclopentadiene (DCPD) and cyclooctatetraene (COT); one or more monomers of a multi-monomer polymer system, such as diols, diamines and epoxides; prepolymers such as partially polymerized monomers still capable of further polymerization; and functionalized polymers capable of forming larger polymers or networks.
The term “activator” means anything that, when contacted or mixed with a polymerizer, will form a polymer. Examples of activators include catalysts and initiators. A corresponding activator for a polymerizer is an activator that, when contacted or mixed with that specific polymerizer, will form a polymer.
The term “catalyst” means a compound or moiety that will cause a polymerizable composition to polymerize, and that is not always consumed each time it causes polymerization. This is in contrast to initiators, which are always consumed at the time they cause polymerization. Examples of catalysts include ring opening metathesis polymerization (ROMP) catalysts such as Grubbs catalyst. Examples of catalysts also include silanol condensation catalysts such as titanates and dialkyltincarboxylates. A corresponding catalyst for a polymerizer is a catalyst that, when contacted or mixed with that specific polymerizer, will form a polymer.
The term “initiator” means a compound or moiety that will cause a polymerizable composition to polymerize and, in contrast to a catalyst, is always consumed at the time it causes polymerization. Examples of initiators include peroxides, which can form a radical to cause polymerization of an unsaturated monomer; a monomer of a multi-monomer polymer system, such as a diol, a diamine, and an epoxide; and amines, which can form a polymer with an epoxide. A corresponding initiator for a polymerizer is an initiator that, when contacted or mixed with that specific polymerizer, will form a polymer.
The term “solvent”, in the context of a healing agent, means a liquid that can dissolve another substance, and that is not a polymerizer.
The term “encapsulant” means a material that will dissolve or swell in a polymerizer and, when combined with an activator, will protect the activator from reaction with materials used to form a solid polymer matrix. A corresponding encapsulant for a solid polymer matrix and for a polymerizer will protect an activator from reaction with materials used to form that specific solid polymer matrix and will dissolve or swell in that specific polymerizer.
The invention can be better understood with reference to the following drawings and description. The components in the figures are not necessarily to scale and are not intended to accurately represent molecules or their interactions, emphasis instead being placed upon illustrating the principles of the invention. Moreover, in the figures, like referenced numerals designate corresponding parts throughout the different views.
In accordance with the present invention a microvascular system includes a solid polymeric matrix and a woven structure in the matrix. The woven structure includes a plurality of fibers and a plurality of microfluidic channels. At least a portion of the microfluidic channels are interconnected. Such reinforced microvascular composites can enable materials systems with unprecedented applications, and can be designed to contain a variety of microvascular network types and sizes—from simple, straight conduits to complex, computer-controlled 3D woven architectures. The reinforced microvascular composites may be formed from commercially available materials, and may be integrated seamlessly with conventional fiber-reinforced composite manufacturing methods.
In accordance with the present invention a microvascular system may be formed from composite materials containing sacrificial fibers and optionally containing reinforcing fibers. Sacrificial fibers may be used to form biomimetic material systems in a reliable manner, and may be used to model, reproduce and/or extend transport functions performed by microvascular systems in nature. Composite materials containing both sacrificial fibers and reinforcing fibers can be used to provide reinforced microvascular composites, such as those described above.
In accordance with the present invention a sacrificial fiber may include a thermally degradable polymeric fiber that degrades at temperatures above those typically used for forming composite materials, but below the typical degradation temperatures of composite materials. A thermally degradable polymeric fiber may include a polymeric fiber matrix and a catalyst in the fiber matrix that lowers the degradation temperature of the matrix polymer to within an appropriate temperature window.
The solid polymer matrix 110 may include a polyamide such as nylon; a polyester such as poly(ethylene terephthalate) and polycaprolactone; a polycarbonate; a polyether; an epoxy polymer; an epoxy vinyl ester polymer; a polyimide such as polypyromellitimide (for example KAPTAN); a phenol-formaldehyde polymer such as BAKELITE; an amine-formaldehyde polymer such as a melamine polymer; a polysulfone; a poly(acrylonitrile-butadiene-styrene) (ABS); a polyurethane; a polyolefin such as polyethylene, polystyrene, polyacrylonitrile, a polyvinyl, polyvinyl chloride and poly(DCPD); a polyacrylate such as poly(ethyl acrylate); a poly(alkylacrylate) such as poly(methyl methacrylate); a polysilane such as poly(carborane-silane); and a polyphosphazene.
The solid polymer matrix 110 may include an elastomer, such as an elastomeric polymer, an elastomeric copolymer, an elastomeric block copolymer, and an elastomeric polymer blend. Examples of elastomer polymers include polyolefins, polysiloxanes such as poly(dimethylsiloxane) (PDMS), polychloroprene, and polysulfides; examples of copolymer elastomers may include polyolefin copolymers and fluorocarbon elastomers; examples of block copolymer elastomers may include acrylonitrile block copolymers, polystyrene block copolymers, polyolefin block copolymers, polyester block copolymers, polyamide block copolymers, and polyurethane block copolymers; and examples of polymer blend elastomers include mixtures of an elastomer with another polymer. Composite materials that include an elastomer as the solid polymer matrix are disclosed, for example, in U.S. Pat. No. 7,569,625 to Keller et al, and in U.S. Application Publication 2009/0191402 to Beiermann et al, which are incorporated by reference. The solid polymer matrix 110 may include a mixture of these polymers, including copolymers that include repeating units of two or more of these polymers, and/or including blends of two or more of these polymers.
The solid polymer matrix 110 may include other ingredients in addition to the polymeric material. For example, the matrix may contain one or more particulate fillers, stabilizers, antioxidants, flame retardants, plasticizers, colorants and dyes, fragrances, or adhesion promoters. An adhesion promoter is a substance that increases the adhesion between two substances, such as the adhesion between two polymers. One type of adhesion promoter that may be present includes substances that promote adhesion between the solid polymer matrix 110 and the fibers 130.
The woven structure 120 includes at least one ply containing a plurality of fibers 130 and a plurality of microfluidic channels 140. The woven structure 120 may include more than one ply containing fibers and microfluidic channels. The woven structure 120 also may include at least one ply containing a plurality of fibers 130 without any microfluidic channels and/or may include at least one ply containing a plurality of microfluidic channels 140 without any fibers. The fibers 130 may be present as tows, also referred to as yarns, which are assemblies of from 100 to 12,000 individual fibers.
The woven structure 120 may be a two-dimensional (2D) structure, in which the ply includes threads oriented in two different directions in substantially a single plane. The woven structure 120 may be a three-dimensional (3D) structure, in which the ply includes threads oriented in two different directions in substantially a single plane, and further includes threads oriented in a third direction that is substantially orthogonal to the plane. An individual “thread” in the woven structure 120 may be a microfluidic channel 140 or a fiber 130, which may be an individual fiber or a fiber tow.
The fibers 130 may include a material having an aspect ratio (diameter:length) of at least 1:10, including at least 1:100 and at least 1:1,000. The fibers 130 preferably include reinforcing fibers that, when added to a solid polymer matrix, increase the strength of the matrix relative to the pure polymer. Reinforcing fibers may include an inorganic and/or an organic material. Examples of fibrous reinforcing materials include graphite fibers, ceramic fibers, metal fibers, and polymer fibers. Examples of graphite reinforcing fibers include Thornel 25 and Modmor. Examples of ceramic reinforcing fibers include metal oxide fibers such as titanium oxide fibers, zirconium oxide fibers and aluminum oxide fibers; silica fibers; and glass fibers, such as E-glass fibers and S-glass fibers. Examples of metal fibers include steel fibers, tungsten fibers, beryllium fibers, and fibers containing alloys of these metals. Examples of polymer fibers include polyester fibers, nylon fibers, rayon fibers, and polyaramid fibers, such as Kevlar 49.
The microfluidic channels 140 may include substantially tubular channels having a diameter less than 1,000 micrometers. The term “substantially tubular” means that the majority of the cross-sectional periphery of the channel through the substrate matrix is curved in shape. Curved can include circular, elliptic, rounded, arched, parabolic and other curved shapes. The average diameter of the substantially tubular channels preferably is from 0.1 to 1,000 micrometers, more preferably is from 10 to 500 micrometers, and more preferably is from 50 to 250 micrometers. The microfluidic channels 140 may have a length of at least 1 centimeter.
Preferably at least a portion of the microfluidic channels 140 have a plurality of interconnects. Interconnects are present wherever a first portion of a channel contacts a second portion of the channel, or wherever a first channel contacts a second channel. In this manner, interconnects connect the channels at a plurality of locations, thus establishing fluid communication between the channels. Microfluidic channels 140 that are interconnected thus form a microfluidic network.
A fluid in the microfluidic channels 140 can flow through the channel and into another channel by way of an interconnect between the channels. If the polymeric matrix includes an inlet port, a fluid delivered through the inlet port can flow through the interconnected microfluidic channels within the polymeric matrix. If the interconnected microfluidic channels form a network, the introduced fluid may at least partially fill the network.
At least a portion of the microfluidic channels 140 can be independent, existing in the matrix 110 without any interconnect with another channel. In one example, all of the microfluidic channels 140 in a microvascular system 100 are independent, and the system does not include a microfluidic network. In this example, any fluid in an individual microfluidic channel 140 is not in fluid communication with a fluid in another microfluidic channel.
The microfluidic channels 140 may include a fluid, such as a gas or a liquid, or they may include a vacuum. The microvascular system 100 may be referred to as an “apomatrix” when the microfluidic channels 140 include a fluid. Without fluid, or with air, microvascular system 100 may be referred to as a “holomatrix”.
The microfluidic channels 140 in the polymeric matrix 110 can affect the structural properties of the matrix, and the type and magnitude of the resulting structural property changes may depend on the properties of the channels and their configuration in the matrix. For example, it may be desirable for the microfluidic channels 140 to have a minimum channel spacing and a maximum channel diameter, which may help to minimize any decrease in the strength of the matrix.
Forming 210 a composite that includes a solid polymeric matrix and a plurality of sacrificial fibers in the matrix may include combining a matrix precursor with a plurality of sacrificial fibers, and then solidifying the matrix precursor to form a solid polymer matrix. The method may further include forming the sacrificial fibers and/or the matrix precursor.
The matrix precursor may be any substance that can form a solid polymer matrix when solidified. The matrix precursor may be substantially homogeneous, or it may include other substances, such as fillers and/or viscosity modifiers. For example, a matrix precursor may include particles that can change the viscosity of the precursor and/or can change the properties of the polymeric matrix formed from the precursor. Examples of particles that may be present in the matrix precursor include plastic particles and non-plastic particles, such as ceramics, glasses, semiconductors, and metals.
In one example, the matrix precursor includes a monomer and/or prepolymer that can polymerize to form a polymer. The sacrificial fibers and optionally other ingredients may be mixed with the monomer or prepolymer. The matrix precursor may then be solidified by polymerizing the monomer and/or prepolymer of the matrix precursor to form the solid polymer matrix.
Examples of monomers and/or prepolymers that can polymerize to form a polymer include cyclic olefins; unsaturated monomers such as acrylates, alkylacrylates (including methacrylates and ethacrylates), styrenes, isoprene and butadiene; lactones (such as caprolactone); lactams; epoxy-functionalized monomers, prepolymers or polymers; functionalized siloxanes; and two-part precursors for polymers such as polyethers, polyesters, polycarbonates, polyanhydrides, polyamides, formaldehyde polymers (including phenol-formaldehyde, urea-formaldehyde and melamine-formaldehyde), and polyurethanes. Polymerization of a matrix precursor may include crosslinking of monomers and/or prepolymers to form an insoluble polymer network. Crosslinking may be performed by a variety of methods, including the addition of chemical curing agents, exposure to light or other forms of radiation, or heating. If a chemical curing agent is used, it may be added to the matrix precursor before or after it is combined with the sacrificial fibers.
In another example, the matrix precursor includes a polymer in a matrix solvent. The polymer may be dissolved or dispersed in the matrix solvent to form the matrix precursor, and the sacrificial fibers and optionally other ingredients then mixed into the matrix precursor. The matrix precursor may be solidified by removing at least a portion of the matrix solvent from the composition to form the solid polymer matrix.
In another example, the matrix precursor includes a polymer that is at a temperature above its melting temperature. The polymer may be melted to form the matrix precursor and then mixed with the sacrificial fibers and optionally other ingredients. The matrix precursor may be solidified by cooling the composition to a temperature below the melt temperature of the polymer to form the solid polymer matrix.
Forming 210 preferably includes contacting the sacrificial fibers with a matrix precursor a temperature of at least 75° C. In one example, forming 210 includes contacting the sacrificial fibers with a matrix precursor that includes a monomer and/or prepolymer, and heating the matrix precursor and sacrificial fibers to a temperature of at least 75° C., for a time sufficient to polymerize the monomer and/or prepolymer. In another example, forming 210 includes contacting the sacrificial fibers with a matrix precursor that includes a polymer that is at a temperature above its melting temperature, where the melting temperature is less than 75° C.
Heating 220 the composite to a temperature of from 100 to 250° C. and maintaining 230 the composite at a temperature of from 100 to 250° C. for a time sufficient to form degradants from the sacrificial fibers may include, for example, placing the composite in an oven. The degradants preferably have an average molecular weight less than 500 Daltons, and preferably are in a gas phase.
Removing 240 the degradants from the composite may include contacting at least a portion of a surface of the composite with a vacuum source. Removing 240 the degradants from the composite may include contacting at least a portion of a surface of the composite with a pressurized fluid, such as a gas. Use of a pressurized fluid or a vacuum may facilitate removal of gaseous degradants. The composite may be maintained at a temperature of from 100 to 250° C. during the removal, or the temperature of the composite may be raised or lowered prior to or during the removal. Removing 240 the degradants from the composite may occur simultaneously with the heating 220 and/or maintaining 230 of the composite, or the removing may occur after the maintaining 230 of the composite.
Interconnects can be formed between microfluidic channels, such as channels 140 of
Optionally introducing 250 a fluid into at least a portion of the microfluidic channels may include any of a variety of methods for introducing a fluid into a microfluidic channel. In one example, the fluid may be injected into one or more channels. In another example, one or more channel openings may be placed in contact with a reservoir of the fluid. The fluid may then flow through the channels through capillary action.
The solid polymer matrix 310 may include a polymeric material, and may include other ingredients in addition to the polymeric material, as described above for solid polymer matrix 110 of
The sacrificial fiber 350 should be strong enough to survive a mechanical weaving process to survive being combined with a matrix precursor. The sacrificial fiber 350 also should remain solid during solidification of the matrix precursor into a polymeric matrix. For solidification by polymerization and/or curing, the fiber 350 preferably should remain solid at temperatures up to 180° C. The sacrificial fiber 350 also should be easily removed from a polymeric matrix by degradation to volatile degradants at higher temperatures. The sacrificial fiber 350 also should have degradation and volatilization temperatures within a narrow range between the highest matrix solidification temperatures and the lowest thermal degradation temperatures of the polymeric matrix (200-240° C.). Preferably, the degradation temperature (TD) of the fiber 350 is at most 250° C. More preferably, the TD of the fiber is at most 220° C., and more preferably is at most 180° C.
Forming 410 a composite that includes a solid polymeric matrix and a woven structure in the matrix may include combining a matrix precursor with a woven structure, and then solidifying the matrix precursor to form a solid polymer matrix. The method may further include forming the woven structure and/or the matrix precursor.
Forming 410 may include forming the woven structure by weaving reinforcing fibers and sacrificial fibers to form a single ply. In one example, an arrangement of warp threads in a first orientation may be held in tension, and weft threads then may be directed sinusoidally in a second orientation through the warp threads. Preferably the second direction is transverse to the first orientation. The warp threads may include reinforcing and/or sacrificial fibers. The weft threads likewise may include reinforcing and/or sacrificial fibers. In this example, the resulting ply is a 2D woven structure.
In another example, an arrangement of warp threads in a first orientation may be held in tension. Weft threads then may be directed in a second orientation over, under and/or through the warp threads, where the second direction preferably is transverse to the first orientation. Z-threads then may be directed through the warp and weft threads, preferably in an orientation that is orthogonal to a plane formed by the weft and warp threads. The Z-threads may be directed through the weft and warp threads sinusoidally. The warp, weft and/or Z-threads may include reinforcing and/or sacrificial fibers. In this example, the resulting ply is a 3D woven structure
Forming 410 may include inserting sacrificial fibers into a ply of woven reinforcing fibers. In one example, a sacrificial fiber is stitched into a woven ply of fibers, such as by repeatedly piercing the ply with a needle attached to a sacrificial fiber, and forming a sinusoidal trace of the sacrificial fiber that traverses the thickness of the ply. In this example, a pattern of one or more sacrificial fibers may be formed along the length and width of the woven ply.
In one example, sacrificial fibers and reinforcing fibers may be arranged into two- or three-dimensional woven preforms. The position, length, diameter, and curvature of the sacrificial and/or reinforcing fibers may be varied to meet desired design criteria.
Forming 410 includes combining the woven structure and a matrix precursor. The matrix precursor may be as described with regard to forming 210 of
In one example, forming 410 includes infiltrating the interstitial pore space between fibers with a low-viscosity thermosetting resin (e.g. epoxy) and curing at elevated temperature. After curing, the sample may be trimmed to expose the ends of the sacrificial fiber.
Heating 420 the composite to a temperature of from 100 to 250° C. and maintaining 430 the composite at a temperature of from 100 to 250° C. for a time sufficient to form degradants from the sacrificial fibers may include, for example, placing the composite in an oven. The degradants preferably have an average molecular weight less than 500 Daltons, and preferably are in a gas phase. Removing 440 the degradants from the composite may include contacting at least a portion of a surface of the composite with a vacuum source or with a pressurized fluid. The heating 420, maintaining 430 and removing 440 may be as described above for heating 220, maintaining 230 and removing 240 of
In one example, the heating 420 may be performed above 200° C., and the maintaining 430 and subsequent removing 440 may provide empty channels and a 3D vascular network throughout the composite.
Optionally introducing 450 a fluid into at least a portion of the microfluidic channels may include any of a variety of methods for introducing a fluid into a microfluidic channel, as described above for introducing 250 of
The introduction of sacrificial fibers into a woven fiber preform can provide seamless fabrication of microvascular composites that are both strong and multifunctional. Preferably the hollow channels produced in the composites are high-fidelity inverse replicas of the original fibers' diameters and trajectories. Use of methods 200 and 400 has yielded microvascular fiber-reinforced composites with channels over one meter in length that then can be filled with a variety of fluids including aqueous solutions, organic solvents, and liquid metals. By circulating fluids with unique physical properties, a new generation of biphasic composite materials is enabled, in which the solid phase provides strength and form while the liquid phase provides interchangeable functionality.
Methods 200 and 400 are examples of a method referred to as Vaporization of Sacrificial Components (VaSC). The VaSC methods can provide composite materials that include microfluidic channels having a range of channel curvatures and diameters, allowing the construction of a wide variety of network architectures. The methods also can provide composite materials that include microfluidic channels that are interconnected and/or branched. Microchannels ranging in size from 20 to 500 micrometers have been created in epoxy matrices using VaSC methods.
As described above with regard to sacrificial fiber 350, sacrificial fibers for use in VaSC methods preferably have a combination of properties, including sufficient strength for weaving and for combining with a matrix precursor using standard composite formation methods, mechanical integrity at temperatures typically used to form composites, and a degradation and volatilization temperature within a narrow range between the highest matrix solidification temperatures and the lowest thermal degradation temperatures of the polymeric matrix.
It has now been discovered that poly(hydroxyalkanoate)s can be modified to produce thermally degradable fibers that can be used successfully as sacrificial fibers in polymeric matrices such as epoxies. These sacrificial fibers preferably are thermally degradable fibers that include a polymeric fiber matrix including a poly(hydroxy-alkanoate), and a metal selected from the group consisting of an alkali earth metal and a transition metal, in the fiber matrix, where the concentration of the metal in the fiber matrix is at least 0.1 percent by weight (wt %).
A poly(hydroxyalkanoate) is an aliphatic polyester having the general structure:
O—C(R1R2)—(CR3R4)x—C(═O)n
where n is an integer of at least 10, x is an integer from 0 to 4, and R1-R4 independently are —H or an alkyl group. Examples of poly(hydroxyalkanoate)s include poly(3-hydroxybutyrate) (P3HB), poly(4-hydroxybutyrate) (P4HB), poly(3-hydroxyvalerate) (PHV), polycaprolactone, poly(lactic acid) (PLA), poly(glycolic acid) (PGA), and copolymers of the monomeric units of these polymers.
Preferably the concentration of the metal in the poly(hydroxyalkanoate) fiber matrix is at least 0.2 wt %, at least 0.5 wt %, at least 1 wt %, at least 2 wt %, at least 2.5 wt %, at least 3 wt %, at least 5 wt %, at least 7 wt %, or at least 10 wt %. The concentration of the metal in the poly(hydroxyalkanoate) fiber matrix may be from 0.1 to 10 wt %, from 0.2 to 7 wt %, from 0.5 to 5 wt %, or from 1 to 3 wt %. Preferably the metal is present in the fiber as MgO, CaO, BaO, SrO, tin(II) acetate, tin(II) oxalate, tin(II) octoate, or scandium triflate (Sc(OTf)3). More preferably the metal is present in the fiber as strontium oxide, tin(II) oxalate or tin(II) octoate.
Poly(lactic acid) (PLA) is a thermoplastic poly(hydroxyalkanoate) that depolymerizes at temperatures above 280° C., forming lactide as a gaseous degradant. Existing epoxy processing protocols, however, can require milder processing conditions, to prevent damage to the epoxy matrix. Although it had been reported that the depolymerization temperature of PLA films could be reduced by blending PLA with calcium oxide or tin reagents, it was not known whether a catalyst incorporated into fibers of PLA could provide depolymerization within an appropriate temperature range, but without degrading the desirable mechanical properties of the fibers below the TD.
When incorporated into a resin matrix, PLA fibers including an alkali earth metal or a transition metal, where the concentration of the metal in the fiber matrix is at least 0.1 w %, preferably may be removed by heating at 200° C. The heating and removal may occur over the course of several minutes to several hours. Preferably the heating and removal are completed in at most 24 hours, at most 5 hours, at most 3 hours, or at most 2 hours.
PLA fibers including an alkali earth metal or a transition metal, where the concentration of the metal in the fiber matrix is at least 0.1 wt %, preferably are compatible with fiber preform fabrication. Preferably the single fiber tension strength of a modified PLA fiber exceeds the threshold stress of 23 MPa applied during automated weaving. Preferably the single fiber tension strength of a modified PLA fiber is at least 30 MPa, at least 50 MPa, at least 75 MPa, or at least 100 MPa.
The clearing of lactide from the channels formed by degradation of PLA fibers including an alkali earth metal or a transition metal typically results in a very low number of obstructions. Hidden defects in the channels may be present, and may be caused by complex channel geometries. Defects may be detected by calculating a theoretical value for pressure drop according to the Hagen-Pouiselle relation and comparing the prediction with a measured pressure head for the channels. A negligible difference from between these values indicates geometric uniformity and substantially complete channel clearing.
An alkali earth metal or a transition metal may be incorporated into a poly(hydroxyalkanoate) fiber through an infusion process such as method 1000. In one example, PLA fibers may be infused with a tin(II) oxalate (SnOx) catalyst present in an aqueous trifluoroethanol (TFE) mixture. Exposing the PLA fibers to a solution of TFE:H2O using a ratio of 60:40 parts by volume (pbv) with 2% SnOx parts by weight (pbw), for a minimum of 24 h yielded sacrificial fibers suitable for VaSC. The catalyst-containing fibers converted to gas at a lower temperature and in less time than did pure PLA fibers, as measured by isothermal gravimetric analysis (iTGA), indicating a lower depolymerization onset temperature.
An alkali earth metal or a transition metal may be incorporated into a poly(hydroxyalkanoate) fiber through a liquid spinning process such as method 1100. In one example, a solution of PLA in dichloromethane containing 10% SnOx pbw was spun through a 0.5 millimeter (mm) spinneret to provide a continuous strand of PLA containing the SnOx catalyst. The catalyst-containing fibers formed by liquid spinning converted to gas at a lower temperature and in less time than did comparable fibers formed by an infusion process, such as method 1000, as measured by thermogravimetric analysis (TGA), indicating a lower depolymerization onset temperature. Cold-drawing the fibers formed from liquid spinning could increase the fiber strength, ensuring that the fibers can be woven using conventional techniques.
Thermally degradable fibers formed by a liquid spinning process such as method 1100 may include a more homogeneous dispersion of catalyst within the fiber than do fibers formed by an infusion process such as method 1000. An improvement in catalyst distribution provides for more of the poly(hydroxyalkanoate) polymer to be in close proximity to a catalyst species, which in turn can result in a more efficient depolymerization and a more rapid removal of the fiber.
A liquid spinning process such as method 1100 may be more efficient in its use of catalyst than an infusion process such as method 1000. For example, a spun fiber formed by method 1100 may include a higher concentration of catalyst than an infused fiber formed by method 1000, even though the spinning liquid and the infusion liquid include the same initial concentration of catalyst. Thus, to achieve a given loading of catalyst in a thermally degradable fiber, a liquid spinning process may require less total catalyst than a comparable infusion process.
Thermally degradable fibers formed by a liquid spinning process such as method 1100 may include a wider variety of depolymerization catalysts than can be included using an infusion process such as method 1000. In one example, infusion of PLA fibers with tin(II) octoate (SnOc) provided fibers with a greasy surface, whereas liquid spinning provided PLA fibers containing SnOc, but with a more desirable non-greasy surface. As the depolymerization temperature of PLA fibers containing SnOc is lower than that of PLA fibers containing SnOx, the liquid spinning method can provide PLA fibers that are readily incorporated into a composite and that depolymerize at a relatively low temperature.
Thermally degradable fibers formed by a liquid spinning process such as method 1100 may reduce the fabrication time of the fibers, and also may reduce the fabrication time of a microvascular system made using the fibers. While an infusion process can be effective in forming thermally degradable fibers, the process can require 24 hours for infusing the catalyst into the fibers, another 24 hours for separating and drying the fibers, and then another 24 hours for degrading and removing the fibers once a composite is formed that includes the fibers. In contrast, thermally degradable fibers may be formed through liquid spinning within 1 hour, the fibers may be dried within 24 hours, and then the fibers may be degraded and removed from a composite within 2 hours.
A method of making a thermally degradable fiber may include other known methods of incorporating an additive into a polymer fiber, such as melt spinning. In the example of melt spinning, the temperature of the material should be maintained below 180° C., the temperature at which PLA can depolymerize in the presence of a catalyst containing an alkali earth metal or a transition metal. On potential advantage of melt spinning PLA fibers containing a depolymerization catalyst is that the fibers may be stronger than comparable fibers formed by infusion or by liquid spinning.
A variety of properties may be obtained with a single microvascular system by selection of one or more fluids for introduction to the microchannels. The variation in properties can be obtained without varying the composite's form factor. Examples of materials properties that may be affected by the fluid in the microchannels of the composites include thermal management, electro-magnetic signature, electrical conductivity tuning, and chemical reactivity.
Thermal management of fiber composites is a highly desirable property for many industrial applications. Nature uses microvascular networks for thermal management by transporting thermal energy to the surface of the organism where heat is more rapidly dissipated. With the introduction of flowing water through a heated 3D microvascular composite, the surface temperature was significantly reduced, potentially increasing the operating temperature of the composite material.
Structures that dynamically change their electro-magnetic (EM) signature are sought both for the ability to transmit information about their physical state, as well as the opposite ability to cloak a surrounding EM field. By filling the channels of a 3D microvascular composite with a ferrofluid, the magnetic field in proximity to the composite was modulated.
Dynamic tuning of electrical conductivity of composites is a desirable property as a means to transmit information and energy. A conductive liquid metal, eutectic gallium-indium (EGaln 75%-Ga 25%-In pbw), was placed inside the channels of a 3D microvascular composite, and the microvascular network was imaged using micro-CT, revealing symmetric placement of electrically conductive channels.
Microvascular networks capable of chemical reactivity are relevant for a range of applications in microfluidics and self-healing systems. As a simple demonstration of a network's ability to perform a chemical reaction, a two-channel mixing network was created. A channel containing a chemiluminescent solution was mixed via fiber interconnects with one containing activator to demonstrate chemical reactivity inside microchannels.
Microvascular system 100 may be a self-healing composite system that includes a solid polymeric matrix 110 and a woven structure 120 in the matrix. The woven structure 120 includes at least one ply containing a plurality of fibers 130 and a plurality of microfluidic channels 140. In one example, the plurality of microfluidic channels 140 includes a first healing agent in the channels. In another example, the plurality of microfluidic channels 140 may include a first plurality of microfluidic channels and a second plurality of microfluidic channels, where the first plurality of microfluidic channels includes a first healing agent in the channels, and where the second plurality of microfluidic channels includes a second healing agent in the channels.
The healing agent may be one or more of a polymerizer, an activator for a polymerizer and/or a solvent. A healing agent in a microfluidic channel may include other ingredients, such as stabilizers, antioxidants, flame retardants, plasticizers, colorants and dyes, fragrances, adhesion promoters, charge-transfer donors, charge-transfer acceptors, or conductive microparticles. The selection of healing agent(s) may be affected by features including fluid rheology, reaction kinetics, and post-polymerised mechanical properties.
Preferably the healing agent includes a polymerizer. For example the healing agent may include a polymerizer that is a monomer, a prepolymer, or a functionalized polymer having two or more reactive groups. For example, a polymerizer may include reactive groups such as alkene groups, epoxide groups, amine groups, phenol groups, aldehyde groups, hydroxyl groups, carboxylic acid groups, and/or isocyanate groups. Examples of polymerizers also include lactones (such as caprolactone) and lactams, which, when polymerized, will form polyesters and nylons, respectively.
In one example, the healing agent includes a polymerizer that is an alkene-functionalized monomer, prepolymer or polymer, which may form a polymer when contacted with other alkene groups. Examples of alkene-functionalized polymerizers include monomers such as acrylates; alkylacrylates including methacrylates and ethacrylates; olefins including styrenes, isoprene and butadiene; and cyclic olefins including dicyclopentadiene (DCPD), norbornene, cyclooctadiene and cyclooctatetraene (COT). Alkene-functionalized polymerizers such as COT and its derivatives, including alkyl-substituted derivatives such as n-butyl-cyclooctatetraene (n-butylCOT), may form conjugated polymers. Examples of alkene-functionalized polymerizers also include diallyl phthalate (DAP), diallyl isophthalate (DAIP), triallyl isocyanurate, hexane dioldiacrylate (HDDA), trimethylol propanetriacrylate (TMPTA), and epoxy vinyl ester prepolymer and polymers. Examples of alkene-functionalized polymerizers are disclosed, for example, in U.S. Pat. No. 6,518,330 to White et al., in U.S. Patent Application Publication No. 2010/0331445, with inventors Wilson et al., and in copending U.S. patent application Ser. No. 13/168,166, with inventors Odom et al.
In another example, the healing agent includes a polymerizer that is an epoxide-functionalized monomer, prepolymer or polymer, which may form an epoxy polymer when contacted with amine groups. Examples of epoxide-functionalized polymerizers include diglycidyl ethers of bisphenol A (DGEBA), such as EPON® 828; diglycidyl ethers of bisphenol F (DGEBF), such as EPON® 862; tetraglycidyl diaminodiphenylmethane (TGDDM); and multi-glycidyl ethers of phenol formaldehyde novolac polymers, such as SU-8. Examples of epoxide-functionalized polymerizers are disclosed, for example, in U.S. Patent Application Publication No. 2011/0039980, with inventors Caruso et al.
In another example, the healing agent includes a polymerizer that is a functionalized siloxane, such as siloxane prepolymers and polysiloxanes having two or more reactive groups. Functionalized siloxanes include, for example, silanol-functional siloxanes, alkoxy-functional siloxanes, and allyl- or vinyl-functional siloxanes. Examples of functionalized siloxanes as polymerizers are disclosed, for example, in U.S. Pat. No. 7,612,152 to Braun et al., and in U.S. Pat. No. 7,723,405 to Braun et al.
In another example, the healing agent includes a solvent as a healing agent. Examples of solvent-based healing agents are disclosed, for example, in U.S. Patent Application Publication No. 2011/0039980, with inventors Caruso et al. In this example, a solvent-based healing agent may restore structural integrity to a composite material by facilitating chain entanglement of polymer molecules. A solvent-based healing agent may facilitate entanglement of polymer molecules of the solid polymer matrix 110 and/or of the fibers 130, provided the fibers are polymeric fibers. The solvent may include an aprotic solvent, a protic solvent, or a mixture of these. Examples of aprotic solvents include hydrocarbons, such as cyclohexane; aromatic hydrocarbons, such as toluene and xylenes; halogenated hydrocarbons, such as dichloromethane; halogenated aromatic hydrocarbons, such as chlorobenzene and dichlorobenzene; substituted aromatic solvents, such as nitrobenzene; ethers, such as tetrahydrofuran (THF) and dioxane; ketones, such as acetone and methyl ethyl ketone; esters, such as ethyl acetate, hexyl acetate, ethyl phenylacetate (EPA) and phenylacetate (PA); tertiary amides, such as dimethyl acetamide (DMA), dimethyl formamide (DMF) and N-methyl pyrrolidine (NMP); nitriles, such as acetonitrile; and sulfoxides, such as dimethyl sulfoxide (DMSO). Examples of protic solvents include water; alcohols, such as ethanol, isopropanol, butanol, cyclohexanol, and glycols; and primary and secondary amides, such as acetamide and formamide.
In another example, the healing agent includes a two-part polymerizer, in which two different substances react together to form a polymer when contacted with an activator. Examples of polymers that can be formed from two-part polymerizer systems include polyethers, polyesters, polycarbonates, polyanhydrides, polyamides, formaldehyde polymers (including phenol-formaldehyde, urea-formaldehyde and melamine-formaldehyde), and polyurethanes. For example, a polyurethane can be formed by the reaction of one compound containing two or more isocyanate functional groups (—N═C═O) with another compound containing two or more hydroxyl functional groups (—OH).
An activator optionally may be present in the solid polymer matrix, or it may be present as a second healing agent in a second plurality of microfluidic channels. Preferably, if an activator is required to polymerize a healing agent that is a polymerizer, the activator is present in a second plurality of microfluidic channels.
The activator may be a general activator for polymerization, or a corresponding activator for a specific polymerizer present in the channels. Preferably the activator is a corresponding activator for a liquid polymerizer present in the channels. The activator may be a catalyst or an initiator.
In one example, corresponding catalysts for polymerizable cyclic olefins include ring opening metathesis polymerization (ROMP) catalysts such as Schrock catalysts (Bazan et al., (1991)) and Grubbs catalysts (Grubbs et al., (1998)). In another example, corresponding catalysts for lactones and lactams include cyclic ester polymerization catalysts and cyclic amide polymerization catalysts, such as scandium triflate.
In another example, corresponding catalysts for the polymerization of silanol-functional siloxanes with alkoxy-functional siloxanes include any catalyst that promotes silanol condensation or the reaction of silanol with alkoxy-functional siloxane groups. Examples of these catalysts include amines and include metal salts, where the metal can be lead, tin, zirconium, antimony, iron, cadmium, calcium, barium, manganese, bismuth or titanium.
In another example, corresponding activators for epoxy polymers include any activator that can react with two or more epoxy functional groups. For example, an epoxy polymer can be formed by the reaction at or below room temperature (for example, 25° C.) of one compound containing two or more epoxy functional groups with another compound containing either at least one primary amine group or at least two secondary amine groups. In these systems, an amine compound can be present in a composite as the activator for an epoxy-functionalized polymerizer.
Corresponding activators for the polymerizer may be two-part activators, in which two distinct substances must be present in combination for the activator to function. In one example of a two-part catalyst system, one part of the catalyst may be a tungsten compound, such as an organoammonium tungstate, an organoarsonium tungstate, or an organophosphonium tungstate; or a molybdenum compound, such as organoammonium molybdate, an organoarsonium molybdate, or an organophosphonium molybdate. The second part of the catalyst may be an alkyl metal halide, such as an alkoxyalkyl metal halide, an aryloxyalkyl metal halide, or a metaloxyalkyl metal halide in which the metal is independently tin, lead, or aluminum; or an organic tin compound, such as a tetraalkyltin, a trialkyltin hydride, or a triaryltin hydride.
In another example of a two-part activator system, a corresponding polymerizer may contain unsaturated polymerizable compounds, such as acrylates, alkylacrylates (including methacrylates and ethacrylates), styrenes, isoprene, and butadiene. In this example, atom transfer radical polymerization (ATRP) may be used, with one of the two components being mixed with the polymerizable compound and the other acting as the initiator. One component can be an organohalide such as 1-chloro-1-phenylethane, and the other component can be a copper(I) source such as copper(I) bipyridyl complex. In another exemplary system, one component could be a peroxide such as benzoyl peroxide, and the other component could be a nitroxo precursor such as 2,2,6,6-tetramethylpiperidinyl-1-oxy. These systems are described in Stevens (1999, pp. 184-186).
In another example of a two-part activator system, a corresponding polymerizer may contain isocyanate functional groups (—N═C═O) and hydroxyl functional groups (—OH). In one example of this type of system, the polymerizer may be a compound containing both an isocyanate group and a hydroxyl group. In another example of this type of system, the polymerizer may include two different compounds, one compound containing at least two isocyanate groups and the other compound containing at least two hydroxyl groups. The reaction between an isocyanate group and a hydroxyl group can form a urethane linkage (—NH—C(═O)—O—) between the compounds, possibly releasing carbon dioxide. This carbon dioxide can provide for the creation of expanded polyurethane foam. Optionally, the polymerizer may contain a blowing agent, for example a volatile liquid such as dichloromethane. In these systems, condensation polymerization may be used, with one of the two components being mixed with the polymerizer and the other acting as the initiator. For example, one component could be an alkylating compound such as stannous 2-ethylhexanoate, and the other component could be a tertiary amine such as diazabicyclo[2.2.2]octane. These systems are described in Stevens (1999, pp. 378-381)
A variety of different woven structures may be present in a self-healing composite system. For example, a self-healing microvascular fiber-reinforced composite may be designed in accordance with a standard Double Cantilever Beam (DCB) mode-I fracture test geometry to exploit the prevalent susceptibility of composite laminate structures to fail by mode-I interlaminar delamination (
The efficiency of consecutive self-healing events in a self-healing composite system may depend on several factors, including adequate delivery of healing agents to the injury site, in-situ mixing to ensure sufficient polymerization, and continued availability of healing agents to a particular region after a damage-heal cycle. Macro-scale delamination region in the fiber-composite DCB geometry and likely real-world applications may benefit from vascular sophistication to ensure sufficient in-situ mixing.
A modified thermal depolymerization/vascularization (VaSC) procedure may be used to make self-healing composite systems having two different microvascular network architectures—a parallel architecture (
While a number of fiber-composite constituents and liquid healing chemistries are available, self-healing microvascular composite systems preferably utilize a well concerted materials system to achieve high efficiency, recurrent in-situ repair. In one example, pre-VaSC composite DCB specimens consisted of 300 μm diameter sacrificial PLA fibers stitched through common aerospace-grade woven textile reinforcement (Style 7781 8H satin E-glass) and infused with a two-part epoxy system exhibiting high-temperature stability (glass transition temperature (Tg)≈150° C.) in accord with the VaSC procedure. An alkyl glycidyl ether diluted bisphenol-A based epoxy resin (EPON 8132) and aliphatic amidoamine hardener (EPIKURE 3046) two-part chemistry satisfied the following performance metrics: low viscosity components (<10 P) such that modest pressurized delivery produces adequate coverage of fracture surface(s), which also facilitates in-situ mixing; the ability to polymerize under non-stoichiometric ratios at ambient temperature; and sufficient bonding/fracture toughness to restore structural integrity. Additionally, both healing agents exhibit excellent compatibility and chemical stability when sequestered in separate vascular networks of an epoxy matrix.
Healing efficiency was evaluated based on the ability of the composite DCB specimen to recover resistance to mode-I crack growth (i.e. interlaminar delamination), and quantified through direct calculation of strain energy release rate (GI). A virgin DCB sample was loaded in quasi-static tension (
Representative load-displacement behavior for a virgin and reference healed specimen is depicted in the graph of
The effect of the VaSC process on GI was assessed to ensure no appreciable loss in crack-growth resistance was incurred. Table 1 lists the results for neat (plain fiber-composites), treated (VaSC conditions, no channels), and both parallel/herringbone vascular configurations.
aone standard deviation
bby average neat value
The treated samples experienced a slight (4%) reduction in GI compared to the neat case; however, the parallel and herringbone specimens exhibited a respective 3 and 10% increase over the neat crack-growth resistance. Scanning electron micrographs (
In-situ self-healing tests were conducted by first filling the dual-vascular networks with their respective healing agent from pressurized reservoirs connected via tubing to micro-dispense tips embedded in the channel orifices. The DCB samples were loaded until the delamination front ruptured the first through-thickness vasculature, whereby an input pressure versus incremental crack-length computer program was initiated (
Maximum healing efficiencies occurred at roughly the same distance (≈20-30 mm) away from the crack tip (
The following examples are provided to illustrate one or more preferred embodiments of the invention. Numerous variations can be made to the following examples that lie within the scope of the invention.
PLA fibers having diameters of 20, 200 or 500 micrometers were obtained from Teijin Monofilament Germany GmbH and used as received. PLA pellets (P1566, Mw=85,000-160,000) for catalyst screening were used as received from Sigma-Aldrich. PLA pellets (Mw=339,000) for forming fibers by solution spinning were used as received from Purac Biomaterials.
Catalysts magnesium oxide (MgO), calcium oxide (CaO), barium oxide (BaO), strontium oxide (SrO), scandium triflate (Sc(OTf)3), tin(II) acetate, tin(II) oxalate, tin(II) octoate were obtained from Sigma-Aldrich unless otherwise noted.
Diglycidyl ether of bisphenol A resin (DGEBA or EPON 828) was used as received from Miller-Stephenson, and the curing agent EPIKURE 3300 was used as received from Hexion. Epoxy samples were prepared using a mass ratio of 22.7 parts per hundred (pph) EPIKURE 3300 to EPON 828.
Trifluoroethanol (TFE) was obtained from Halogen Inc. Other chemicals were all obtained from Sigma-Aldrich unless otherwise noted.
Thermogravimetric analysis (TGA) was performed on a Mettler-Toledo TGA851e, calibrated with indium, aluminum, and zinc standards. For each experiment, the sample (approximately 10 mg) was weighed (±0.02 mg) in an alumina crucible. For dynamic measurements, the mass loss was recorded during a heating cycle over the temperature range of 25 to 650° C. at a heating rate of 10° C./min. For isothermal experiments, the temperature was ramped from 25 to 240° C. at a rate of 50° C./min and subsequently held at 240° C. for 2 h.
Differential scanning calorimetry (DSC) was performed on a Mettler-Toledo DSC 821e using a nitrogen atmosphere to measure heat flow (positive exothermal) from 25 to 450° C. at a heating rate of 10° C./min.
Fiber surface morphology and fiber removal in epoxy matrices were imaged using a Leica DMR Optical Microscope at various magnifications. Image) software was used to measure fiber diameters from acquired images for each batch of fibers produced and to measure the fraction of PLA fiber removed.
Analytical gel permeation chromatography (GPC) was performed on a Waters 515 HPLC pump, a Viscotek TDA Model 300 triple detector array, a Thermoseparations Trace series AS100 autosampler, and a series of 3 Waters HR Styragel columns (7.8×300 mm, HR3, HR4, and HR5) in THF at 30° C. The GPC was calibrated using monodisperse polystyrene standards, and all molecular weight data were reported as polystyrene equivalents.
Environmental Scanning Electron Microscopy (ESEM, Philips XL30ESEM-FEG) was used to image cross-sections of the holomatrix and to image empty channels. SEM images were acquired after sputter-coating the sample surface with carbon or gold-palladium, and were collected using backscattered electrons. Selected area elemental analysis was performed by EDS (Energy Dispersive X-ray Spectroscopy, attached to the SEM) with a 20 kV electron source and spot size of 3.0 nm.
Mass spectra were recorded on a 70-VSE C in ES+mode through the University of Illinois Mass Spectrometry Laboratory, SCS.
1H-NMR spectra were obtained using a Varian 400 spectrometer in the VOICE NMR laboratory at University of Illinois. Spectra were referenced to the residual proton solvent (CDCl3) peak.
An Xradia BioCT (MicroXCT-400) was used to image the apomatrix at 40 keV (8 W power and 200 pA current) at a 4× objective for 5 s exposure times. Rotation intervals were 0.25° for a complete 360° scan. Images were visualized in 3D with XM3Dviewer and reconstructed in 3D using XMReconstructor. Reconstructed images were reproduced in Amira to enhance the color and contrast.
The tensile strength of spun fibers was measured at room temperature on an Instron Machine (Instron Mini-44). For each test sample, a fiber with the gauge length of 30 mm was clamped between pneumatic grips, and the test was performed in a displacement controlled mode using rate of 10 mm/min. The corresponding tension load was measured using a 500 N load cell. Engineering stress and strain were calculated and plotted using the load-displacement data.
Wide angle X-ray Scattering (WAXS) analysis was conducted through the Materials Chemistry Laboratory at the University of Illinois. WAXS data were collected on a Bruker General Area Detector Diffraction System (GADDS) equipped with a P4 four-circle diffractometer and HiStar multiwire area detector. A Bruker M18×HF22 rotating anode generator operating at 50 kV and 40 mA supplied the Cu Kα graphite monochromatized incident beam. WAXS analysis of fibers was performed on several fibers mounted parallel to each other an aluminum mount, where the sample to detector distance was 8.5 cm. Two frame series were collected at 20 settings of −10, 0, and 10 degrees. The first frame series was collected with the fibers aligned vertically and the second series was collected with the fibers in horizontal alignment. The combined 2D images were then integrated and combined into 1D patterns.
Catalysts that had been reported to decrease the depolymerization temperature of PLA were screened. The catalysts investigated included earth metal oxides, tin-containing compounds, and rare metal triflates. The catalysts listed above were screened by the reported literature procedure (Fan, Y. et al. Polymer 2004, 45, 1197-1205), except that commercial PLA pellets were used. Commercial PLA pellets were dissolved in chloroform (1 g/mL) and the test catalysts were blended into the viscous solution (approximately 10 wt % to PLA). The mixture was vigorously stirred for 1 h to disperse the catalysts uniformly. The dispersed mixture was cast on a petri dish and allowed to dry before rinsing with methanol. A thin film was obtained on the petri dish and was dried under vacuum (0.2 torr) for 24 h. The vacuum-dried films were then removed from the petri dish and manually cut into pieces for TGA experiments.
PLA blended with tin(II) oxalate began to depolymerize at a temperature approximately 80° C. lower than unmodified PLA (
Catalysts were incorporated into PLA sacrificial fibers by a modified literature procedure (Quirk, R. A. et al. Macromolecules 2000, 33, 258-260). Catalysts were evenly dispersed (2 wt %) in a miscible mixture of trifluoroethanol (TFE, a PLA solvent) and water (a PLA nonsolvent). The PLA fibers were soaked in the stirred solvent/catalyst mixture at 37° C. for a period of different times (2-24 h), removed and subsequently air-dried. In some cases, rhodamine 6G (0.5 wt %) was incorporated into PLA fibers using the same fiber treatment procedure, for improved visualization during macroscopic imaging.
In order to survive conventional composite fabrication, the catalyst should not significantly change the mechanical properties of the fibers. Both strontium oxide and tin(II) octoate degraded PLA fiber properties. Strontium oxide, as well as other earth metal oxides, formed strongly basic hydroxides upon contact with water, which deteriorated the PLA fibers. Surface damage was evident by visual inspection, where the oxide caused either a reduction of the fiber's cross-sectional area or branching of the fiber. Tin(II) octoate, an oily liquid, had poor dispersibility in the solvent mixture and resulted in greasy fibers.
The PLA fiber was soaked in the TFE/water mixture, which caused rapid polymer swelling at the surface, allowing for infiltration of catalysts into the fiber. The effects of solvent composition, fiber-solvent soaking time, and post-soak treatment by isothermal TGA were evaluated, and these data were correlated with observations of fiber removal. These experiments were performed using PLA fibers with a diameter of 500 micrometers, and tin(II) oxalate concentration in the solvent mixture was fixed at 2 wt %.
The chemically treated PLA fibers were embedded in an EPON 828: EPIKURE 3300 matrix that was cured in a silicone rubber mold using the standard protocol. Sacrificial fibers were held straight in RTV Silicone molds before filling the mold with epoxy. Epon 828 epoxy resin and a cycloaliphatic amine curing agent Epikure 3300 were mixed at a ratio of 100:22.7 pbw and degassed until air bubbles ceased to form. The post-curing cycle involved heating the specimens at 82° C. for 90 minutes followed by 150° C. for an additional 90 minutes.
The resulting holomatrices were carefully polished before thermal treatment so that fiber ends were exposed. The holomatrices were heated in a sealed vacuum oven (Fisher Isotemp 283) at a constant temperature (ranging from 180 to 220° C.) under vacuum (1 torr). The fraction of fiber removed (defined as the ratio of empty channel length over the full fiber length) was measured for each sample after heating for 2 h.
Solvent composition (the ratio of TFE to water) was investigated so that maximum catalyst incorporation was achieved without dissolving the fiber. Control experiments demonstrated the TFE/water treatments lacking a catalyst had no effect compared to untreated fibers. When catalyst was present in the soaking bath, TGA showed faster PLA mass loss with an increased amount of TFE in the mixture.
The fiber soaking time also affected the treatment efficiency, presumably because longer time allowed more catalysts to diffuse into the fiber. PLA fibers were soaked in the solvent/tin(II) oxalate mixture for varying amounts of time (2-24 h), and subsequently analyzed the depolymerization reaction. Isothermal TGA showed a significant increase in the rate of PLA fiber weight loss with increased soaking time.
In a literature procedure, polymer swelling was reversed by the addition of a large excess of nonsolvent (water). In the present example, adding a large amount of water resulted in a decrease in the rate and extent of the thermal depolymerization compared to the simple solvent evaporation. Thus, after soaking the fiber in a solvent/catalyst mixture, the fiber was removed and dried in the air which allowed the solvent to evaporate and the catalyst particles to become immobilized. Under otherwise identical processing conditions, fibers that were dried in the air had a significantly larger fraction of thermally depolymerized fiber than those treated with water. Thus, an optimum method to quench catalyst infusion was simple air-drying.
For PLA fibers (diameter: 500 micrometers), the optimum processing procedure involved soaking PLA fiber in a solvent mixture containing 60% TFE and 40% H2O dispersed with 2 wt % tin(II) oxalate for 24 h and air-drying the fiber afterwards. For PLA fibers of different diameters (20 micrometers and 200 micrometers), the optimum processing procedures involved the same steps with different solvent composition and fiber soaking time (Table 2).
The thermal depolymerization behavior of these chemically treated PLA fibers in an epoxy matrix was compared to that of the untreated one under the same thermal conditions. A 5 cm long, 200 micrometer diameter PLA fiber treated with tin(II) oxalate using the optimized fiber treatment protocol was completely removed after heating in vacuo at 180° C. for 20 h, yielding an empty microchannel. In contrast, a large portion of solid fiber remained for the untreated PLA fiber.
The PLA fiber molecular weight change during the tin(II) oxalate assisted catalytic depolymerization process was monitored by GPC analysis. PLA fibers (diameter 500 micrometers) treated with catalyst were placed in a vial and heated at 240° C. in a sealed oven. Thermal depolymerization products at each designated time point were extracted and analyzed using GPC. The vapor condensation collected from heated fibers was analyzed by ESI-MS and 1H NMR.
The entire process was performed inside a fume-hood. A desired length of fiber 10 m) of desired diameter (i.e. 500 micrometers, 200 micrometers) was wound on a customized red with minimum surface contact. The reel was attached to a digital mixer (Eurostar, IKA Labortechnik) and then lowered in a narrow neck beaker filled with 800 mL of treatment solution (480 mL TEE, 320 mL deionized H2O and 16 g tin oxalate, 40 mL Disperbyk 187 (Byk Chemie)). In cases where fibers are dyed pink/red, 1 g of Rhodamine 6G was added to the solution prior to fiber addition. The beaker was suspended in a temperature-controlled water bath on a programmable hot plate with an external temperature probe. The solution was agitated with a digital mixer (Eurostar, IKA Labortechnik), driving the reel at 350RPM for 24 h at 37° C. The entire apparatus was sealed using saran wrap to prevent evaporation of TFE. After 24 h, the reel containing wound fibers was removed and allowed to air dry inside a fume hood for 1 h at which time the fiber was unwound from the reel and wound on spindles for later use.
A PLA solution was prepared by dissolving 6 g of PLA pellets in dichloromethane at room temperature, and then removing solvent to provide a solution volume of 35 mL. Catalysts (tin(II) oxalate particles or tin(II) octoate liquid) were blended into the viscous PLA solution to provide a 10 wt % tin equivalence to PLA. The mixture was stirred for half an hour to disperse the catalyst, resulting in a spinning solution.
A spin chamber was pre-heated to 55° C., and 10 mL of the spinning solution was transferred to the chamber. The solution was conditioned in the spin chamber for 5 minutes, and then conditioned outside the chamber for additional 5 minutes before extrusion, allowing the solution to become more concentrated. The spinning solution was then extruded at 55° C. through the chamber at an extrusion speed of 8 cm/hr. The solution passed through a spinneret having a diameter from 0.2 mm to 1 mm, forming a single fiber. Two heating chambers below the spinneret provided additional heat to further evaporate the solvent. The extruded fiber filament was collected on a Teflon bobbin without applying additional stress, and was then air-dried at 50° C. The diameter of the fibers after drying was dependent on the diameter of the spinneret used in the spinning process. A spinneret diameter of 0.25 mm provided a final fiber diameter of 0.14±0.02 mm, a spinneret diameter of 0.50 mm provided a final fiber diameter of 0.42±0.03 mm, and a spinneret diameter of 1.00 mm provided a final fiber diameter of 0.75±0.05 mm.
The mechanical properties of the spun PLA fibers could be changed by cold-drawing the spun fibers. Cold-drawing fibers may provide an increase in tensile strength, which is theorized to be due to alignment of the individual polymer chains within the fiber during the drawing process. WAXS analysis of PLA fibers that were cold-drawn after being spun is consistent with an increase in polymer chain alignment within these fibers, as the degree of orientation of pure spun PLA fiber (no catalyst) increased from 0% when no drawing was performed to 23% when cold-drawing was performed. Spun PLA fibers were drawn to different draw ratios, and their failure strengths were studied by a single fiber tension test, with the test results plotted in
In order to study the catalyst distribution on the fiber, SEM images were obtained of a cross-section of the holomatrix where the sacrificial fiber was embedded. Tin(II) oxalate was visible along the edges of the interface. Elemental information revealed the presence of tin-rich regions (white spots) at the fiber interface, compared to the area of epoxy matrix. The apomatrix was further imaged by MicroCT (
To examine the effect of fiber curvature on Vaporization of Sacrificial Components (VaSC), a fiber was wrapped around a small, cylindrical piece of room temperature cured epoxy. Specifically, a 200 micrometer fiber was wound around a 2 mm diameter plug to complete a 180° turn. The fiber was embedded in an epoxy matrix followed by thermal depolymerization process resulting in a completely empty 180° curved channel. The image was stitched together from multiple optical microscope pictures using the open source software package Fiji (http://pacific.mpi-cbg.de/wiki/index.php/Fiji).
Fiber removal typically occurred over the period of 24 h, with 95% of the material removed in less than 6 h. At these temperatures, the initially clear and colorless epoxy matrix was slowly discolored upon exposure to oxygen. Under vacuum (1 torr) samples displayed less color change going from colorless to golden-amber. This discoloration occurred primarily at the surface and had no significant impact on mechanical properties of the sample.
The following types of fibers were analyzed for their behavior at elevated temperatures:
Each type of fiber was embedded in an EPON 828:EPIKURE 3300 epoxy thermoset that was cured in a silicone rubber mold using the standard protocol. The cured epoxy thermoset composites were carefully trimmed before thermal treatment to expose fiber ends. The composites were heated in a sealed vacuum oven (Fisher Isotemp 283) at 200° C. under vacuum (1 torr). The fiber removal fraction was measured as the ratio of empty channel length over the full fiber length for each sample at time intervals of 1 h, 2 h, 4 h and 8 h. Fiber removal data were averaged for each type of fiber over 25 epoxy thermoset samples with 1 inch fiber lengths.
PLA fibers (Teijin Monofilament, Germany) were immersed in a stirred 800 mL solution of TFE:H2O 60:40 (pbv) containing 16 g SnOx and 0.5 g rhodamine 6G and 50 mL Disperbyk 187 (Byk Chemie). The solution was continuously stirred for 24 h at 37° C. Fibers of increasing diameter required longer periods of catalyst infusion, up to 24 h, in order to achieve sufficient removal.
Fibers of diameter 200 micrometers and 500 micrometers were tested in direct tension using an Instron Mini-44 test frame with a load cell capacity of 500 N. A special fixture was designed to hold the fibers straight and precisely aligned with the axis of the test frame. The fibers were loaded using pneumatically controlled grips. The tests were performed in displacement-controlled mode at a constant rate of 5 mm/min until complete fiber failure. Five samples were tested for each 200 and 500 micrometer diameter for both untreated and treated PLA fibers. Two sets of treated fibers were evaluated corresponding to treatment times of 12 h and 24 h.
The entire 3D fiber preform including sacrificial PLA fibers was woven by 3TEX, Inc. using an automated 3D weaving machine in a 3WEAVE non-crimp orthogonal pattern. The 3D fiber preform consisted of 2 warp and 3 fill layers of 276 tex (g/km) E-glass roving interwoven with 331 tex S-glass in the z-direction. A portion of the 3D textile, four central rows in the z-direction, was replaced with 500 micrometer diameter sacrificial PLA fibers. Additionally, five layers of a 2D plain weave E-glass fabric (47.5 g/m2) were then placed above and below the 3D preform to yield roughly 325 micrometers of non-vascular skin surfaces.
Both the hand-woven (
The automated machine woven specimens were infused with an Epon 862/Epikure 3300 resin system mixed at a stoichiometric ratio of 100:24.8 by weight. The hand-woven specimens were infused using an Epon 815C/Epikure 3300 resin system mixed at a stoichiometric ratio of 100:22.7 by weight.
Epon 862 epoxy resin was first degassed for 1 hour before mixing with curing agent Epikure 3300 (100:24.8 pbw), and then again degassed for 45 minutes. Vacuum was applied at 724 torr using a vacuum pump (Welch® DryFast Tuneable Chemical-Duty Vacuum Pump—model 2032B-01) to infiltrate the 3D fiber preform with resin. Once the entire fiber preform was saturated with resin, the inlet line was clamped shut while the vacuum continued to run for at least 16 h during room temperature curing of the 3D composite. The post-cure cycle for both resin systems consisted 1.5 h at 82° C. and 1.5 h at 150° C. in a programmable oven (Thermo Scientific Lindberg/Blue M). The 3D woven composite specimens were then demolded, and the ends were cut using a diamond-tipped wet saw to ensure complete exposure of the sacrificial fiber cross-section before the clearing procedure.
Cured epoxy samples containing sacrificial fiber were placed into a sealed vacuum oven (Fisher Isotemp 283) at 200° C. for 48 h under vacuum (1 torr). Afterwards, samples were cooled to ambient temperature under vacuum before exposing them to atmospheric conditions. If the procedure occurs without vacuum, the channels clear, but the epoxy turns from colorless to brown, most likely the result of oxidation from entrapped oxygen in the composite. With vacuum applied, the color change is much less severe and samples are typically amber or golden brown after the clearing procedure.
The pressure drop (ΔP) calculations were performed using the well-established Hagen-Poiseuille relation:
Here, μ denotes the dynamic viscosity of the fluid, L and d signify the channel length and diameter, respectively, and Q represents the volumetric flow rate.
The above relation assumes that the flow is laminar viscous and incompressible, which occurs through a straight channel of constant circular cross-section whose length is substantially larger than its diameter. Based upon measurements taken from optimal microscopy, the four 500 micrometer microchannel profiles in the thickness direction were closely approximated by trigonometric functions of the form:
z
1,3(x)=A0 sin(ψx)z2,4(x)=A0 cos(ψx).
Here, x is the coordinate along the length axis; Δ0 denotes the amplitude; and ψ represents the wavenumber calculated by ψ=2π/λ, where λ is the wavelength. Using the integral arc-length formula, a composite specimen 42 mm long, was calculated to have a single microchannel length of about 76 mm for both the sine and cosine counterparts.
Various pressure heads were applied using a large basin of H2O, so that the decrease in height resulting from fluid flowing through the channels was negligible. Taking the dynamic viscosity of water at 20° C. to be 1.002 cP, the calculated pressure drop through the four microchannels was compared with the applied pressure head as shown in the graph of
DMA testing was performed on TA Instruments RSA III equipment using a three point bending fixture. A linear heating rate of 3° C./min was applied from 25-200° C. The material response was monitored at a constant frequency of 1 Hz. The storage modulus and tangent δ were calculated for the given temperature range. The tests were performed on neat epoxy specimens (Spon 828/Epikure 3300) cured using the manufacturer recommended curing cycle (1.5 h at 82° C. and 1.5 h at 150° C.) and on samples post-cured at 200° C. for 48 h to investigate the effect of prolonged heating. The dynamic mechanical properties are listed in Table 3. The error listed represents the standard deviation obtained from five samples.
Active cooling measurements were accomplished using infrared imaging of the top face of the 3D-microvascular composite. The bottom face of the composite was placed on a copper plate subjected to a constant temperature boundary condition. A thin layer of thermally conductive grease (OmegaTherm) was applied to the bottom face of the composite to eliminate contact problems and create a thermally conductive interface between the copper plate and the composite. A resistive heater was attached to the copper plate (Watlow 120V, 200 W) and controlled with a Watlow Series 942 microprocessor to maintain the copper plate temperature. A feedback control thermocouple was placed on the top of the plate to monitor the temperature of the plate throughout the experiment.
Infrared images were taken using a DeltaTherm 1560 infrared camera with 320 by 256 array of indium antimonids IR detectors. Data was recorded at one frame per second using DeltaVision software. Each data set contained a 2D temperature field of the specimen surface. A region was selected, as shown by the white lined box on the IR image, to average the temperatures of the pixels within this region. The change in temperature within this region was monitored to find the active cooling performance of this composite. The coolant of choice was water, which was pumped through the microchannels at a flow rate of 10 ml/min. The coolant was introduced into the sample at room temperature (21° C.) at a constant flow rate maintained using screw driven syringe pump (KD scientific, Model 210). Coolant flow through the microchannels of the 3D composite resulted in a temperature drop of about 40° C. in 60 seconds.
Field maps around the 3D woven capillary manifold, which was filled with a FerroTec® ferrofluid, were imaged using a magneto-optical imaging technique. A bismuth-substituted yttrium iron garnet (Bi-YIG) indicator film was placed on the top surface of the sample and an external magnetic field H=100 Oe (7960 A/m) was applied perpendicular to the indicator plane to align the magnetic moments of the nanoparticles in the ferrofluid.
The resulting inhomogeneous magnetic flux modulated by the average magnetic moments in the capillaries was imaged using a Zeiss polarized light microscope. The stronger field from the segment of capillaries closest to the indicator film caused a larger Faraday rotation in the garnet and was observed as a local increase of intensity. Intensity versus field calibration allowed us to measure the local field strength yielding approximately 7 Oe (˜560 A/m) increase of H, as indicated by the bright spots in
Commercially available Coleman Illumisticks® containing a chemiluminescent system, were judiciously opened and the two components: a reactive dye solution and an activator solution were separated and stored in glass vials. An interconnected Y-shaped channel was created by wrapping two 500 micrometer fibers around one another for two-thirds of the length, where at one end they were separated by an angle of 45°. The channel geometry was maintained by holding the fibers under tension in an RTV Silicon mold. The fibers were cast in solid resin (Epon 862, Epikure 3300) and cleared leaving behind a mixing channel with two open ports at one end merging into a single inter-connected channel.
In the top channel, a syringe containing the dye solution was connected via a 25-G needle and in the lower channel a syringe containing the activator solution was introduced. The two were mixed by continuous addition from each syringe driving liquid into the central mixing channel. As mixing occurred, chemiluminescence was detected in the central portion and continued until the end of the channel indicating the e microvascular networks can be used to induce chemical reactivity.
The 3D microvascular composite specimen was placed in an electrical circuit in series with an ammeter and a DC power supply unit with current and voltage control options. A voltmeter was placed in parallel to the composite specimen that acts as the resistor in the circuit. Both voltage and current were varied using the DC power supply in order to calculate the resistance of the composite, with and without a conductive phase in the microchannels. Each measurement was repeated three times and the averages have been reported. Initial measurements were made on the composite with empty microchannels. The glass fiber composite served as a non-conductive resistor with a measured resistivity of about 104 Ω-cm (Conductivity: 10−4 S/cm). The microchannels were then filled with a liquid, eutectic Gallium-Indium alloy and electrical wires were embedded in the liquid alloy followed by solidification process using cooling. Measurements were made for the current flow through a single channel and it was observed to be highly conductive with an electrical conductivity of 4000 S/cm.
A single fiber measuring just over 0.5 meters in length was woven through a 3D glass fabric preform using hand-weaving process. The VARTM process was used to infuse the 3D preform with epoxy resin (EPON 862, EPIKURE 3300). The composite was subjected to VaSC process as described in earlier sections for fiber evacuation.
Sacrificial (PLA) fibers were prepared in a fume-hood according to a modified procedure. 300 μm diameter PLA fibers (Teijin Monofilament, Nextrusion GmbH) were first wound on a customized reel, avoiding significant overlap of the fibers to maximize free surface exposure. 360 mL of deionized H2O were combined with 40 mL of Disperbyk 187 (Byk-Chemie GmbH) in a glass container that was subsequently sealed and manually agitated/shaken until a uniform solution was obtained. A 1000 mL glass beaker was suspended (13 mm from the bottom) in a water-filled crystallization dish (190×100 mm 600 mL, Kimax®), which rested on a programmable digital hot plate (Ecotherm™ HS40, Torrey Pines Scientific) set to 37° C. at 450° C./hr. Temperature feedback was accomplished via an external probe (HS30-600, Torrey Pines Scientific) also suspended in the bath. 440 mL of Trifluoroethanol (TFE) (Halocarbon Products Corp.) were combined with the 400 mL H20/Disperbyk 187 solution in the 1000 mL beaker and stirred by hand until uniform. 1 g of Rhodamine 6G dye (Sigma-Aldrich) was added to the solution and mixed by hand until fully dissolved. The PLA fiber reel was attached to a digital overhead stirrer (Caframo BDC 3030) and lowered into the solution filled beaker. While rotating the fiber wound reel at 400RPM, 13 g of Tin (II) Oxalate (SnOx) (Sigma-Aldrich) was slowly added to the solution to avoid agglomeration of the powdered catalyst. The pH was adjusted to a value between 6.8-7.2 via titration of an aqueous solution of sodium hydroxide (NaOH, 20 wt. %). A customized lid was secured to the 1000 mL beaker, forming a tight seal to prevent evaporation of the solution. The SnOx catalyst infusion/treatment process was run for 24 hrs, after which the fiber wound reel was removed from the solution bath, drip-dried at room temperature (RT) for 5 min, and then placed in a 35° C. oven (Fisher Scientific Isotemp 750G) for 24 hrs. The dried monofilament was then unwound from the reel and was ready for use as “sacrificial” material.
An adapted VaSC procedure was used to create microvascular networks in a woven fiber-reinforced composite laminate. Eight plies of an 8-harness satin weave E-glass fabric (Style 7781, Fibre Glast Developments Corp.) were stacked in a [90/0]8 layup sequence and tensioned across a 280 mm×280 mm PVC cross stitch frame (SF11, Q-Snap). A CAD generated, printed-paper template was secured to the top fabric layer via painters tape and aligned such that the long axis of the DCB geometry was oriented parallel to the 0° ply. The 300 μm diameter PLA fibers of Example 19 were hand-stitched through the paper template/textile reinforcement in respective parallel (
Epoxy resin infiltration (Araldite LY/Aradur 8605, 100:35 by wt., Hunstman Advanced Materials LLC) was achieved via Vacuum Assisted Resin Transfer Molding (VARTM) at 38 Torr (abs) until complete fabric wetting and then decreased to 76 Torr (abs) for 36 hours at room temperature (RT) until resin solidification. The fiber-composite panel was post-cured for 2 h at 121° C. plus 3 h at 177° C. to produce a glass-transition temperature of ≈150° C.
Microvasculature was created by depolymerizing/sublimating the SnOx catalyst infused PLA fibers following a Vaporization of Sacrificial Components (VaSC) procedure. Composite DCB samples were cut using a diamond-blade wet saw from the 4 mm thick panel to approximately 30 mm wide and 180 mm long (80 mm ETFE, 100 mm stitched), exposing the sacrificial fiber cross sections. Air-dried composite samples were then placed in an evacuation oven (Jeio Tech Co., Ltd. OV-11) for 36 h at 200° C. under 12 Torr (abs) vacuum. The evacuated, microvascular samples were removed, air-cooled to room temperature, and trimmed to final areal dimensions of 27 mm wide by 155 mm long (60 mm ETFE, 95 mm vascular). The vasculature was then flushed with water, followed by an ethyl alcohol rinse, and finally compressed air.
In-situ fluid delivery parameters, namely input pressure versus crack length, were calculated using a combined theoretical/experimental scaling approach based on dimensionality of variables in the well-established Hagen-Poiseuille relation:
In this expression, ΔP is the pressure drop associated with a given mass-volumetric flow rate m-Q, based on fluid density p, and dynamic viscosity μ, through a cylindrical channel of diameter d, and length L.
While this analytical solution to the Navier-Stokes equations is valid for viscous, laminar flow of an incompressible fluid through a straight circular tube of constant cross section, the relative dimensionality, i.e. exponent, of variables in the above relation was assumed to hold for flow through the undulating vasculature which satisfied all remaining criteria. By experimentally measuring the mass flow rate of H20 through both parallel and herringbone microvascular networks under a static pressure head, given the same tubing/micro-nozzle connections employed in-situ, the required input pressures for the more viscous healing agents over varying channel lengths were determined through dimensionally consistent scaling. For example, flow through a channel one-fifth as long with a fluid ten times as viscous (same density) would simply double the pressure drop through a channel of identical size.
Microvascular channel lengths were accurately determined by measuring the amount of sacrificial fiber woven into the textile preform and subtracting the portion cut away during DCB sample fabrication. Both (resin/hardener) channel lengths in the parallel network were nearly identical at 295±4.5 mm. In the herringbone network design, the resin channel was longer at 420±0.3 mm than the channel containing hardener at 390±2.8 mm. Additionally, although not directly relevant to the input pressure estimation, the total channel/void volume fraction was calculated for each network design in the vascularized portion of the DCB geometry (95 mm×27 mm×4 mm): parallel 0.41%, herringbone 0.56%. The herringbone void volume fraction was roughly √2 times the parallel amount owing to the 45° diagonal variations along the length.
Healing agent viscosities were measured on a computer-interfaced rheometer (TA Instruments AR-G2) using 25 mm parallel aluminum plates (gap size between 0.5-1.0 mm) over a range of shear rates from 0.1 to 100 (1/s) with ten data acquisition points per decade. Both liquid components exhibited Newtonian flow behavior, indicated by a linear shear rate versus shear stress relationship. Dynamic viscosity (μ) was calculated as the slope of this line, where the resin component (Epon 8132, Momentive) had a measured viscosity of 7.4 P and the hardener component (Epikure 3046, Momentive) had a measured viscosity of 3.1 P, both of which were slightly higher but within 10% of the upper bound published in the manufacturers technical datasheets.
Healing agent densities were determined by delivering 5 mL of each component into a glass scintillation vial using a high-precision, computer controlled syringe pump (KDS Scientific, Model 210P) and weighing the respective quantities on a laboratory analytical balance (Denver Instrument Company A-250). The calculated densities: 8132 (resin) 1.07 g/cm3, 3046 (hardener) 0.91 g/cm3, were in good agreement with manufacturers provided data.
Given the measured physical quantities for the two-part healing system and based on the theoretical/experimental dimensionally consistent scaling procedure outlined above, a series of pressure input curves to produce a constant total volumetric flow rate of 100 μL/min were generated for both microvascular networks at two delivery ratios: 1R:1H, 2R:1H (by volume). Since the channel lengths shortened upon fracture-induced rupture and the crack-propagation rate was not necessarily constant across the entire prescribed delamination length, the stepped (decreasing) nature of the input curves was designed to achieve consistent fluid delivery by serving as a manual adjustment/correction every 5 mm.
In-situ pressurized fluid delivery was accomplished via two electronic fluid dispensing units (Ultimus™ V, Nordson EFD) controlled with an in-house LabView (National Instruments, v.2009) program. Precision stainless steel (310 μm OD, 150 μm ID) micro-dispense tips (part #7018424, Nordson EFD) are attached via polypropylene Luer fittings (part #s 51525K291-51525K141, McMaster Carr) to laboratory tubing (R-3603, Tygon and connected to 5 cc fluid syringe barrel reservoirs with internal pistons (part #7012096, Nordson EFD). Initially, a small amount of pressure (0.03 MPa) was applied to each syringe barrel to fill the entire tubing and micro-nozzles with the respective healing agents. One micro-nozzle for each healing agent was then inserted into a respective channel orifice and pressure was re-applied (parallel: (R) 0.17, (H) 0.10 MPa, herringbone: (R) 0.24, (H) 0.14 MPa) to fill the entire vascular network until liquid was expelled from the respective exit port and the pressure was removed. The remaining micro-nozzle was then inserted into the open orifice, resulting in a closed, filled system. Upon quasi-static, displacement controlled (5 mm/min) tensile loading also executed via LabView, and subsequent microvascular network rupture as a result of crack advance, the stepwise pressure input profiles were initiated and progressively decreased throughout the prescribed delamination regime. Upon reaching the crack termination point for the current test, the pressure was removed and the sample was unloaded (25 mm/min), carefully detached from the mechanical wedge grips (Instron 2716), and allowed to heal at the prescribed conditions (48 h@30° C.) in a constant temperature oven (VWR Scientific 1450D). A slight static pressure head (ΔPs) remained on each syringe barrel during the healing process to prevent backflow of chemically contaminated components that could potentially polymerise inside the microchannels and inhibit further healing cycles (Δa=30, 50, 70 mm: ΔPs=0.25, 0.18, 0.11 kPa, respectively).
Brass hinges (25 mm×25 mm, McMaster-Carr) were bonded to the outer faces of the self-healing composite system of Example 21 on the pre-crack end using a high-strength structural adhesive (Scotch-Weld™ DP 460, 3M™) and allowed to cure for 48 h at RT to ensure sufficient bond-strength before testing. One side (4 mm×155 mm) of the DCB sample was spray painted white (Shock White Acrylic, Montana Gold) and allowed to air-dry at RT for 48 h. Delineations of 5 mm were marked on both the painted side and coincident top edge beginning at the interior pre-crack interface and extending along the vascular segment (95 mm) to the end of the sample.
The mode-I strain energy release rate (GI), a measure of crack-growth resistance, was calculated according to ASTM International. ASTM D5528: Standard Test Methods for Mode I Interlaminar Fracture Toughness of Unidirectional Fiber-Reinforced Polymer Matrix Composites (2007) and/or according to Hashemi, S. et al. Journal of Materials Science Letters 2, 125-129 (1989). GI calculations from discrete (5 mm delineations) and continuous crack-length measurements were performed according to Modified Beam Theory (MBT):
where P is the applied load, δ is the crosshead displacement, b is the specimen width, a is the total crack length (a=a0+Δa), and |Δ| is a correction factor to account for non-zero rotation at the delamination front. This correction factor, |Δ|, is defined as the absolute value of the x-intercept of the line generated from a least squares plot of the cube root of compliance, C1/3≡(δ/P)1/3 versus crack length (a).
GI calculations using the area method were performed according to the expression:
where Δ∪ is the change in internal work or strain energy due to elastic bending in the cantilever arms, and derived from first energy principles as the area under the load-displacement curve at a particular incremental crack length (Δa):
Thus, healing efficiency was defined as the ability of a healed sample to recover crack-growth resistance:
For the MBT calculations; GIVirgin was the average virgin strain energy release rate over a delamination length, and GIHealed was the average healed strain energy release rate over the same delamination. For the area method, as the specimen width and incremental crack length were equivalent, as the healing efficiency definition reduces to a canonical expression involving only the ratio of areas under the load-displacement curves:
While various embodiments of the invention have been described, it will be apparent to those of ordinary skill in the art that other embodiments and implementations are possible within the scope of the invention. Accordingly, the invention is not to be restricted except in light of the attached claims and their equivalents.
This application is a divisional of U.S. application Ser. No. 13/721,801 filed Dec. 20, 2012, which is a continuation-in-part of U.S. application Ser. No. 13/416,002 entitled “Micro-Vascular Materials And Composites For Forming The Materials” filed Mar. 9, 2012, which claims the benefit of U.S. Provisional Application No. 61/451,698 entitled “Micro-Vascular Network Materials And Composites For Forming The Materials” filed Mar. 11, 2011. Each of these applications is incorporated by reference in its entirety.
This invention was made with government support under contract number(s) FA9550-05-1-0346, FA9550-09-1-0686, FA9550-10-1-0255 and 2008-ST-061-ED002, awarded by the Air Force Office of Research and the OFA/Department of Homeland Security. The government has certain rights in the invention.
| Number | Date | Country | |
|---|---|---|---|
| 61451698 | Mar 2011 | US |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 13721801 | Dec 2012 | US |
| Child | 14607759 | US |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 13416002 | Mar 2012 | US |
| Child | 13721801 | US |
