MXPA01008270A - Flexible fabric from fibrous web and discontinuous domain matrix - Google Patents

Abstract

A composite having a plurality of filaments arranged in a fibrous web that is held together in a unitary structure by a domain matrix. The domain matrix comprises a plurality of matrix islands that individually connect, or bond, at least two filaments, to thereby hold the filaments in a unitary structure. Portions of the filament lengths within the unitary structure are free of matrix islands, causing the domain matrix to be discontinuous. The composite possesses a greater flexibility than coated structures. The composite may be formed into cross-plied structures. A method of making the composite is also disclosed.

Description

FLEXIBLE FABRIC AND FIBROUS TISSUE DISCONTINUOUS DOMAIN MATRIX BACKGROUND OF THE INVENTION FIELD OF THE INVENTION The present invention relates sterr.as as continuous layers of integrated fiber material domains that form matrix islands, and more particularly to a method for developing continuous systems of fiber layers held together with matrix islands and continuous system compositions of crosslinked fiber layers with matrix islands. The fiber layer systems of the present invention offer high resistive composite products with bending and strength characteristics especially useful in flexible articles highly resistant to impacts. BACKGROUND OF THE INVENTION Articles designed to resist ballistic impact, such as bulletproof vests, helmets, body armor, plate armor and other equipment for the police and the army, structural members of helicopters, aircraft, ships, and Vehicle panels as well as portfolios containing high strength fibers are known in the art. Known high strength fibers include aramid fibers, fibers such as (poly) phenylenediamine terephthalamide, ultra molecular weigh polyethylene * •• sa. »---. • -., *. .-, "... high", graphite fibers, ceramic fibers, nylon fibers, glass fibers and the like. The fibers are generally encapsulated and integrated into a continuous structure of matrix material, and, in some cases, are joined with rigid face layers to form complex composite structures. An armor must provide protection against ballistic projectiles such as bullets and other modern projectiles or projectiles. However, a body armor, bulletproof vests, etc., can be rigid and restrict the movement of the person using them. Composite articles resistant to bullets have been reported in Harpell et al. U.S. Patent Nos. 4,403,012; 4,501,856 and 4,563,392. These patents disclose networks of high strength fibers in matrices composed of olefin polymers and copolymers, unsaturated polyester resins, epoxy resins, and other curable resins below the melting point of the fiber. While these compounds offer effective ballistic resistance, A.L. Lastni et al, "The Effect of Resin Concentration and Laminating Pressures on Kevlar Fabric Bonded With Modified Phenolic Resin" (The effect of resin concentration and pressures on fabrics laminated together with Kevlar modified phenolic resin), Technical Report NATICK / TR 84/030, of June 8, 1984, has disclosed that an interstitial resin that encapsulates and binds the fibers of a fabric, reduces the ballistic resistance of the resulting composite article. Accordingly, there is a need to improve the structure of composite articles to effectively utilize the properties of high strength fibers. U.S. Patent No. 4,623,574, to Harpell et al., Filed on January 14, 1985, and assigned in a joint manner discloses simple composite products comprising high strength fibers integrated in an elastomeric matrix. Surprisingly, the simple composite structure shows an outstanding ballistic projection compared to a simple composite product that uses rigid matrices. Whose results are reported here. Particularly effective are simple composite articles employing polyethylene and polypropylene with ultra-high molecular weights such as those disclosed in U.S. Patent No. 4,413,110. Compound products having continuous domains are disclosed in the art, generally restricting the percentage of resin to be at least 10% by volume of the fiber content. U.S. Patent No. 4,403,012 discloses a matrix in the preferred range of 10 to 50% by weight of fibers. U.S. Patent No. 4,501,856 discloses a preferred fiber network content of 40 to 85% by volume of the composite product. The North American patent number 4, 563,392 does not disclose any range for the amounts of a matrix component. It is desirable to maintain a volume and / or percent fiber passage as high as possible within a resulting composite product to increase the increase in ballistic resistance. U.S. Patent Nos. 5,061,545 and 5,093,158, both pooled, disclose an article composed of fibers / polymers with a polymer matrix distributed non-uniformly, and a method for making the composite article. These patents focus on a fibrous web having a network of unidirectional fibers, and a matrix composition distributed non-uniformly but continuously in the main plane of the fiber network. The network of fibers becomes embedded in the composition of is evenly distributed, the matrix composition remains continuous, holding all the fibers of the fibrous tissue. The patent discloses a polymer composition of non-uniform distribution together with a fibrous tissue in such a way that a patterned surface is offered, causing parts of the resulting combined fabric to have larger amounts of polymer than other portions. Thus, the total amount of polymer required to maintain the integrity of the fabric impregnated with polymers was reduced. The patents further disclosed that the thick areas that provide the integrity of the polymeric layer preferably offer a continuous area along the surface of the fibrous / polymeric composite article. Other patents, such as U.S. Patent No. 4,623,574, have shown the difficulty of preparing a composite article made of a fabric fabric within a polymeric matrix. In table 6, sample 12, when a high amount of fibers was used, the sample did not show consolidation and could not be tested. U.S. Patent 3,683,048 discloses a composite article comprising several parallel fibers held together by resinous bridges between two or more adjacent filaments. The cost and quality of the fabrics also affect the availability of armor. The cost of a conventional fabric rises dramatically as the yarn denier falls. In addition, both ballistic performance and flexibility improve as the density per area of individual layers decreases. COMPENDIUM OF THE INVENTION The present invention is a composite article comprising a fibrous tissue and a discontinuous domain matrix, preferably a polymeric composition. The domain matrix offers fixed matrix islands or anchoring points within the fibrous tissue to join portions of the fibrous tissue into a unitary structure. The matrix islands can hold from two filaments within the fibrous tissue, or they can hold all of the filaments of fibrous tissue, including having the shape of a continuous chain (highly elongated domain). With sufficient number, size, shape and distribution of matrix islands, the individual filaments within the fibrous tissue form a unitary structure. A fibrous tissue is a layer defined by a plurality of fibers. Typically, the layer is thin and defines a surface having a depth of at least one filament, preferably, the fibrous tissue is a tape or layer wherein the fibers are unidirectional. By unidirectional, we understand that the fibers are parallel to each other within the fabric or that the fibers extend along a given directional axis, without splicing. Matrix islands are defined as retaining anchor points and preferably join two or more filaments together, with each island of a separate or discontinuous matrix of other matrix islands forming a spatial distribution. Collectively, the matrix islands constitute a domain matrix that unites the fibrous tissue as a flexible unitary structure. The matrix islands can be distributed within the domain matrix in regular and / or random patterns. The amount of polymeric material of the domain matrix is sufficiently small to cause areas of fibers without matrix to be present (hereinafter "uncoated fiber" or "uncoated filaments"). Fiber fabrics can be folded to form flexible panels. The present invention includes a composite article consisting of several fibers, preferably arranged along a single directional axis, wherein the various fibers are essentially parallel to each other, and matrix islands crossing at least a portion of the various fibers sufficient to maintain and preferably join the plurality of fibers in a unitary structure, where the various fibers have an out-of-plane flexibility. In addition, the present invention includes a method for making an article composed of a fibrous tissue bridged with matrix islands comprising the steps of arranging various fibers in a layer, and placing a plurality of matrix islands within the various fibers in such a way that each matrix island crosses a sufficient portion of the plurality of fibers to maintain and preferably join the plurality of fibers into a unitary structure. The composite article of the present invention can form a flexible tape, preferably unidirectional (also known as uni-tape) which can be used as a precursor in conventional textile processes of tape laying or filament winding. Transverse shapes of the composite article may vary with use, such as for example the shape of a flat citation, elliptical shapes, circular shapes, and special shapes that are preferable for given textile processes such as braiding and weaving. Flexible fibrous tissue layers can be combined to form folded products. The articles composed of fibrous tissue and matrix domain, as well as the method of the present invention maintain tissue integrity and yet result in a composite article with significant advances in terms of volumetric ratio in fiber and polymer compared to the technique previous. These structures are ballistically efficient and highly flexible, with the ability to transmit water vapor. BRIEF DESCRIPTION OF THE DRAWINGS Figure 1 is a top view of a preferred fibrous tissue with random matrix islands forming a unidirectional structure; Figure IA illustrates the domain matrix of Figure 1; Figure 2 is a top view of a domain matrix of non-random matrix islands that join filaments in a unidirectional structure; Figure 3 illustrates a top view of the shape of the matrix islands along the length of two unidirectional tapes folded at 90 ° C of Figure 1; Figure 3A illustrates a top view of the shape of a single matrix island; Figure 4A shows an enlarged isometric view of a folded 0/90 composite structure from two layers of the structure of Figure 1; Figure 4B shows a top view of figure 4A; Figure 4C shows a side view of Figure 4A; Figure 5A shows a side view of Figures 4A, 4C with an outer film layer; Figure 5B shows an enlarged isometric view of Figure 5A; Figure 6 shows a top view of a folded structure of the unidirectional tapes. Figure 7 is an illustration of a preferred method for making the composite article of the present invention; Y Figure 8 is an illustration of an alternate preferred method for making the composite article of the present invention. DETAILED DESCRIPTION OF THE INVENTION The present invention focuses on a composite article having filaments that define a fibrous tissue fixed by a domain matrix. The composite article preferably contains several filaments in the form of parallel fibers, known as a set of parallel filaments, fixed in the domain frame. The domain matrix consists of several matrix islands, preferably made of a polymeric material, spatially distributed within the domain matrix. The matrix islands anchor together and maintain the filaments of the fibrous tissue as a unitary structure. These anchors fix the position of the individual filaments of the fibrous tissue in relation to each other, and yet allow folding of the combination. The total volume of the matrix islands over a given area of a fibrous tissue taken as a fraction of the fiber volume defines the volumetric density density of the domain matrix Vm / Vf). The matrix islands of the domain matrix are not physically connected to each other, outside through a filament material. As such, the domain matrix comprises a discontinuous polymeric material or "islands", however, since the matrix islands permanently anchor specific fiber locations, the domain matrix is a fixed structure. The discontir- a structure of the domain matrix allows a higher volumetric percentage of fibers in the composite article than in the case of a continuous matrix composition. In addition, a robust structure is created, that is, the domain matrix joins the fibers into an easily handled unitary structure without showing a tendency to separate or spread. The discontinuous structure of the domain matrix produces isolated domains within the fibrous tissue and within the products manufactured from it. Isolated domains that leave larger sections of uncoated fibers, or without matrix material, are necessary to increase the folding of the composite article. The amounts of domain matrix employed should be small enough to provide a non-coated filament segment in the fibrous tissue and resulting products, and may include amounts that promote matrix-free areas. The volumetric ratio (Vm / Vf) can be up to 0.5 as the fibers and the pciimeric material compatibly produce areas of uncoated filaments; however, the domain matrix is present in amounts of volumetric ratio of about 0.4 or less, more preferably from about 0.25 to about 0.02 and more preferably from about 0.2 to about 0.05. By providing a spatial distribution of the matrix islands, extremely high volumes of fibers can be incorporated to form a structure having improved physical integrity during processing and use, such as handling and cutting the composite article, and stacking tissue tape unidirectional fibrous. The resulting fibrous tissue structure maintains the flexibility of the combined uncoated fibers within the fibrous tissue. By maintaining their integrity and the ability to be managed, we understand that the fibrous polymeric composite article retains its structure without yarn separation during processing and use. More than a layer of fibrous fabric bonded with resin can accumulate to form several laminated products of multiple layers, such as 0/90, + 45 / -4S, + 30 / -30, 0/60/120, 0/45 / 90/135, etc. These multilayer composite laminate products are resistant to impacts and more specifically to ballistic impacts. Each section of fibrous tissue of the composite article of the present invention has a spatial distribution of polymer or matrix islands, which preferably hold together two or more filaments of fibrous tissue together, providing areas with polymeric material and areas without polymeric material. Figure 1 illustrates a composite article 10 comprising a fibrous tissue 12 and a domain matrix 14. Fibrous tissue 12 consists of oriented nidirectional filaments 16. The domain matrix 14, shown separately in Figure IA as comprising individual matrix islands 18 is structure within the fibrous tissue 12, and defined there by the fibrous tissue 12. As shown in FIGS. 1 and 1A, even though the matrix domain 14 joins the individual filaments 16 between them, is the location of the filaments 16 which defines the location of the islands of hue 18. As previously stated, the domain matrix 14 is formed from the combination of the matrix islands 18 and it exists as a discontinuous matrix of polymeric material. The uncoated filaments 16 fixed by matrix islands 18 allow a dimensional flexibility of fibrous tissue not previously known. The structure of the present invention allows the transmission of gases and liquids. In addition, areas without matrix can be filled with other resins to achieve the desired properties or characteristics of the composite article. In one embodiment, the matrix islands 18 are spaced randomly and / or irregularly within the fibrous tissue 12, over the entire length of the fibrous tissue 12. Each matrix island 18 retains the relative positions of at least two filaments 16 , and may retain the relative positions of up to all of the filaments 16 in the unidirectional tape. The matrix islands 18 preferably have dimensions such that they are no thicker than a set of filaments 16 within a fabric 12, since the additional polymeric material has a tendency to fill the empty areas of the fibrous tissue 12. Collectively, the arrangement randomization of the matrix islands 18 provides a support domain matrix 14 which maintains the fibrous tissue 12 in a unitary structural configuration.

Different sections of the fibrous tissue 12 may possess varying amounts of polymeric material in terms of size and / or spatial density of the matrix islands 18. However, a given fibrous tissue 12 generally has an average size, a size distribution, a distance average between matrix islands ÍS and other statistical characteristics of matrix islands 18 over the entire length of the composite article offering specific properties. The sizes of the matrix islands 18 must also be relatively small in relation to the size of the impact projectile, since smaller size matrix islands 18 better control the designed spatial position of closely spaced parallel filaments locally on the projectile scale that make an impact The matrix islands 18 must be small compared to the desired radius of curvature from a specific web. Uncoated filaments 16 between the matrix islands 18 allow the flexibility of the fibrous tissue 12 while areas constituting the matrix islands 18 remain as anchoring points which maintain several filaments within the fibrous tissue 12 in a fixed relationship therebetween. Preferably, the average size of the tint islands is less than about 5 mm in at least one direction, more preferably less than about 3 mm, preferably still greater, less than about 2 mm, and especially less than 1 mm . Although areas with the polymer composition are not as flexible as areas without matrix, the areas with the polymer composition preferably provide flexibility to the fibrous tissue 12. Most of the length of the filaments 16 has no preference matrix, and consequently a fibrous tissue 12 of the present invention can move more easily than a fabric where the fibers are fully embedded in a matrix. In another embodiment, shown in Figure 2, the matrix islands 18 are spaced regularly within the fibrous tissue 12 within discrete domain matrix areas 14 across the entire length of the fibrous tissue 12. Over extended equal lengths, shown as length A, of the fibrous tissue 12, the spatial density of the matrix islands 18 remains generally constant. However, over shorter lengths of the fibrous tissue 12, as shown as length B, the spatial density of the matrix islands 18 can vary greatly. Domain matrices 14 can be continuous from one side to the other of a unidirectional tape as shown in Figure 2. The ribbon of the matrix islands 18 generally follows the surface line of the fibers, as shown in Figure 3, with the matrix island 18 in the upper layer filament 16 shown in solid and the matrix island 18 in the lower layer filament 20 shown in phantom line. The size of the matrix islands 18 between the filaments 16, on average, is a sufficient amount to join adjacent layers and to maintain the structural integrity in use. The size, shape and spatial density of the matrix islands 18 within the fibrous tissue, or prepreg, dictate the formation of uncoated filaments within a final product. The shape of the matrix islands 18 provides the amount of tolerable flexibility for a given section of fibrous tissue 12, while still retaining functional attributes as anchoring points for additional filaments 16. Although the size of individual matrix islands 18 generally does not is critical, there must be a sufficient amount of matrix composition on an anchor point, on average, to provide structural integrity and strength for a given use. The spatial distribution of the matrix islands 18 offers the structural integrity in a distortion perpendicular or at another angle with respect to the direction of the filaments 16, while the spatial density provides characteristics other than the unified fibrous tissue 12. As shown in FIG. Figure 3, the shape of the individual matrix island 18 is elongated with its longitudinal dimension parallel to the length of the filament 16. The elongated shape of the matrix islands 18 is caused by a wetting phenomenon, when the small droplets of matrix (suspension of latex in water or matrix solution) touch the filaments. The small drop then extends into the space between the filaments, trying to reduce the surface energy. The aspect ratio, or ratio between length and width (1 / a) shown in Figure 3A, of the matrix islands 18 may be useful in a wide range of quantities for particular uses, including non-exclusively proportions between approximately 35 : 1 and about 1: 1, from about 20: 1 to about 1: 1, from about 10 to about 1: 1, and / or from about 3 to about 1: 1. Although elongated shapes are more common, regular and irregular shapes can be employed, examples of which include, without limitation, regular shapes such as donuts or atolls, rectangles, squares, circles, ellipses, etc., as well as irregular shapes such as islands asymmetrical With cross filaments 20 used in a folded structure 30, the matrix island 18 extends over the length of both filaments 16 and 20 and fixes them. The diameter of the matrix island 18 at the intersection point 22 between the filament 16 and the cross filament 20 determines the adhesion of the unidirectional panels (or fibrous fabrics) when formed in folded configurations. The folded and unfolded tape forms of the present invention offer porous structures of high flexibility. When the unidirectional tape having a polymeric material protruding on one side is folded with a second unidirectional tape, individual particles of polymeric material are pressed on both unidirectional tapes. The resin, which preferably flows along the direction of the fiber of each unidirectional tape, forms a cross shape. On each surface of an elongated domain, the elongated domain is formed with the long axis parallel to the direction of the fiber. With a panel 0/90 or + 45 / -45, elongated domains are superimposed and oriented at a right angle between them. Figures 4A-4C illustrate a preferred embodiment of the unidirectional tapes of Figure 1 formed in a folded configuration. As can be seen in Figure 4A, the ribbons 32 and 34 form layers with their respective filaments perpendicular to each other, for example in an array 0/90, +30/60 or + 45 / -45. Matrix islands 18, which form a domain matrix 14, join the filaments 16 into unidirectional tapes 32 and 34, as well as join the tapes 32 and 34 together. Additional tapes can be placed on any of the sides or on both sides of the tapes 32 and 34 with the same orientation or with another orientation, as for example in a -45 / + 45 configuration. Figure 4B is a top view of Figure 4A showing the upper ribbon 32 with matrix islands 18 in a discontinuous pattern there. Figure 4C is a side view of Figure 4A showing the filaments 16 of the upper belt 32 and lower belt 34 joined by matrix islands 18. As shown in Figures 5A and 5B, in some cases, it is desirable to have a surface film on the panels to reduce the possibility of trapping individual fibers or filaments and damaging the panels in the case of normal handling. Figure 5A shows a side view of an upper belt 32 and a lower belt 34 formed of filaments 16 placed between two films 100 and 102. The belts 32 and 34 and the films 100 and 102 are joined together by matrix islands 18 which collectively form a domain matrix of the composite article. Figure 5B is an enlarged isometric view of Figure 5A, showing the ribbons 32 and 34 fixed by matrix islands 18, with the upper 100 and lower films 102 also fixed by the matrix islands 18. For maximum flexibility, the films are preferably thin and joined by stitches with the tapes. Figure 6 shows a folded structure with the matrix islands 18 extending across the width of the ribbon 34. The extended matrix islands 18 remain discontinuous therebetween even with the application of a second ribbon 32. Highly elongated narrow matrix domains 14 that cross as straight lines all the parallel fibers in a unidirectional tape are perpendicular to the set of fibers or present an angle (F), preferably from about 10 ° to about 170 °, more preferably about 30 ° to approximately 150 °, or as curved lines that include patterns created by circles, ellipses, ovals and multiple geometric figures. The high strength fibers of the present invention preferably have a tensile modulus of about 160 g / denier and a tenacity of at least 7 g / denier in a suitable domain or polymer matrix 14. The polymer composition of the matrix of domain 14 may comprise an elastomer, thermoplastic elastomer, thermoplastic, thermosetting, and / or combinations or mixtures thereof, preferably, the polymer composition comprises an elastomeric matrix material. The fiber is tested in accordance with ASTMD 2256 using 4D belting and cord fasteners on an Instron RTM test machine at an elongation of 100% / minute. It is preferred to have an elastomer composition with a tension modulus of less than 138,000 kPa (20,000 psi), preferably less than 41,400 kPa (6000 psi), in accordance with that measured according to ASTM D638-84 at a temperature of 25 ° C. filaments 16 of the present invention are elongated bodies of considerable longitudinal dimension compared to their transverse dimensions of width and thickness, the term fiber includes not exclusively a monofilament, multifilament, yarn, strips, and similar structures having regular or irregular transverse areas. The fibrous tissue 12 for purposes of the present invention comprises any group of fibers useful for making a unidirectional tape and / or folded structures. Preferred fibrous tissue 12 comprises highly oriented ultra high molecular weight polyethylene fiber, highly oriented ultra high molecular weight polypropylene fiber, aramid fiber, polyvinyl alcohol fiber, polyacrylonitrile fiber, polybenzoxazole fiber (PBZO), polybenzothiazole (PBZT), fiberglass, ceramic fiber or combinations thereof. The ultra high molecular weight polyethylenes are generally understood as including molecular weights of about 500,000 or more, more preferably about one million or more. And especially from approximately 2 million to an amount of approximately 5 million. The tension modulus of the fibers, in accordance with that measured with an Instron tensile testing machine, is usually at least about 300 g / denier, preferably at least 1000 g / denier and more preferably at least less approximately 1500 g / denier. The tenacity of the fibers is usually at least about 15 g / denier, more preferably at least 25 g / denier, preferably even higher at least 30 g / denier, and especially at least about 35 g / denier. The ultra-high molecular weight polypropylenes are within a range of weight average molecular weights of about 750,000 or more, preferably about 1 million, or more, and especially greater than about 2 million. Since polypropylene is much less crystalline than polyethylene and contains pendant methyl groups, the toughness values that can be achieved with polypropylene are generally substantially lower than the corresponding values for polyethylene. Proper tenacity for polypropylene can be within a range of at least 8 g / denier, with a preferred tenacity being at least 11 g / denier. The tension module for polypropylene is at least about 160 g / denier, preferably at least about 200 g / denier. The melting point for the polypropylene is generally raised to several degrees by the orientation process, such that the polypropylene fiber preferably has a main melting point of at least about 168 ° C, more preferably, so less about 170 ° C. An aramid fiber is formed mainly of aromatic polyamides. Aromatic polyamide fibers having a modulus of about 400 g / denier and a tenacity of at least about 18 g / denier are useful for incorporation into composite articles of the invention. Exemplary aramid fibers include (poly) phenylenediamine terephthalamide fibers commercially produced by DuPont Corporation of Wilmington, Delaware under the tradenames of Kevlar® 29, Kevlar® 49 and Kevlar® 129. Polyvinyl alcohol fibers (PV-OH) are useful in weight average molecular weights of at least about 100,000, preferably 200,000, more preferably between about 5,000,000 and about 4,000,000 and especially between about 1,500,000 and about 2,500,000. Usable PV-OH fibers should have a modulus of at least about 60 g / denier, preferably, at least 200 g / denier, more preferably at least about 300 g / denier, and a tenacity of at least about 7 g / denier, preferably at least about 10 g / denier, and more preferably at least 14 g / denier, and especially at least about 17 g / denier. PV-OH fibers having a weight average molecular weight of about 500,000, a toughness of at least about 200 g / denier and a modulus of at least about 10 g / denier are especially useful for the production of resistant composite products to the bullets. PV-OH fibers having such properties can be produced, for example, by the process disclosed in commonly assigned U.S. Patent No. 4,559,267 to Kwon et al. Details regarding polybenzoxazole (PBZO) and polybenzothiazole (PBZT) filaments can be found in "The Handbook of Fiber Science and Technology; Volume II, High Technology Fibers ", Part D, edited by Menachem Lewin which is incorporated herein by reference: Polyacrylonitrile (PAN) fibers having a molecular weight of at least about 400,000, and preferably at least 1,000,000 they can also be used PAN fibers having a tenacity of at least about 10g / denier and an energy to break of at least about 22 July / g are particularly useful PAN fibers having a molecular weight of at least about 400,000 a tenacity of at least about 15-20 g / denier and an energy to break of at least about 22 July / g are especially useful for the production of articles resistant to bales, such fibers are disclosed, for example, in U.S. Patent No. 4,535,027 For the purposes of the invention, a fibrous layer comprises at least one fibrous fiber fabric either alone or with a matrix. they include one or more filaments 16. The term fiber refers to an elongated body, the longitudinal dimension of said body being much greater than the transversal dimensions of width and thickness. Accordingly, the term "fiber" includes monofilament, multifilament, web, strip, strand and other forms of discontinuous or cut to similar fibers having regular or irregular cross sections. The term fiber includes several of any of the elements mentioned above or a combination thereof. The cross sections of the filaments for use in this invention may vary widely. They can be circular, flat or elongated in terms of their cross section. They may also have irregular or regular multilobal cross sections having one or more regular or irregular lobes projecting from the linear or longitudinal axis of the fibers. It is particularly preferred that the filaments have a substantially circular, flat or elongate, especially circular, cross section. The fibers can be placed in fibrous fabrics having various configurations, by fibrous tissue we mean a network of various fibers placed in a predetermined configuration or several fibers grouped together to form a twisted or untwisted yarn, said yarns are placed in a predetermined configuration . For example, they can be formed as felt or another nonwoven, woven or woven fabric (taffeta point, woven mat, satin fabric, etc.), placed in a parallel set, in layers or formed in a fabric or any of several techniques. conventional Among these techniques, for application of ballistic resistance, we prefer to use parallel assemblies in which the fibers are flattened to extend the individual filaments in essentially a single layer. Cut-resistant applications can use other configurations of fiber assemblies. In accordance with a particularly preferred network configuration, the fibers are aligned in a unidirectional manner such that they are substantially parallel to one another along a common fiber direction. Continuous length fibers are especially preferred even when oriented fibers and having a length of about 7.6 to about 30.4 cm (from about 3 to about 12 inches) are also acceptable and are considered "substantially continuous" for the purposes of this invention. Both the thermosetting and thermoplastic resin particles, alone or in combination, can be used with the present invention. Preferred thermosetting resins include epoxies, polyesters, acrylics, polyimides, phenolics, and polyurethanes. Preferred thermoplastic resins include nylon, polypropylenes, polyesters, polycarbonates, acrylics, polyimides, polyetherimides, polyaryl ethers, and polyethylene and ethylene copolymers. Thermoplastic polymers have an improved environmental resistance, increased fracture toughness, and higher impact resistance compared to thermosetting materials. Fibrous fabrics that have thermoplastic domain matrices have an extended shelf life, and greater resistance to environmental storage problems. The high viscosity of the thermoplastic polymers does not affect the discontinuous application of the polymeric material in the fibrous tissue 12. Even in significantly increased amounts, the thermoplastic fibrous fabrics of the present invention are flexible structures. Fibrous fabrics containing thermosetting domain matrices 14 are relatively flexible and tacky prior to the reaction. The domain matrices may contain polymeric material from polymer powders, polymer solutions, polymer emulsions, cut filaments, thermosetting resin systems, and combinations thereof. Applications of these polymeric materials can be by spraying, small drops, emulsion, etc. when cut filaments are used, heat and / or pressure can be used to consolidate the single and / or multi-layer tape panel, and the cut filaments must melt at a temperature lower than that of the filaments 16 in the single tape. For example, a flexible structure can be prepared using a fibrous tissue 12 of 215 denier Spectra® 1000 fibers together with a powder either Kraton® of 1650 or with a powder of LDPE (low density polyethylene) or LLDPE (linear polyethylene) low density) with molding carried out at a temperature of 120 ° C. As such, the need for a polyethylene film, commonly used with individual commercial elements, can be eliminated. The pre-molded fibers may, if desired, be pre-coated with a polymeric material (preferably an elastomer) before being fixed in accordance with that described above. The elastomeric material that can also be used as the matrix has a voltage modulus, measured at a temperature of about 23 ° C, of less than about 138,000 kPa (20,000 psi) preferably less than 41,400 kPa (6000 psi). Preferably the tension modulus of the elastomeric material is less than about 34,500 kPa (5000 psi), and with special preference less than 17,250 kPa (2,500 psi) to provide even better performance. The glass transition temperature (Tg) of the elastomer of the elastomeric material (in accordance with what is evidenced by a sudden drop in the ductility and elasticity of the material) remains flexible under field or work conditions, including less than about 25 ° C, or less than about 0 ° C. The glass transition temperature (T, 3) of the elastomer may be within a range of less than about -40 ° C or less than about -50 ° C if desired. The elastomer must have an elongation at break of at least 50%. Preferably, the elongation at break is at least about 100%, and more preferably at 150%. Any suitable elastomeric material for creating domain matrices can be used for the present invention. Representative examples of suitable elastomers of the elastomeric material have their structures, properties and formulations together with crosslinking procedures which appear in summary form in the Encyclopedia of Pol mer Science, volume 5, "Elastomers-Synthetic" ( John Wiley and Sons Inc., 1YES4). For example, any of the following materials may be used: polybutadiene, polyisoprene, natural rubber, ethylene-propylene copolymers, ethylene-propylene-diene terpolymers, polysulfide polymers, polyurethane elastomer, chlorosulfonated polyethylene, polychloroprene, plasticized polyvinyl chloride using dioctyl phthalate or other plasticizers well known in the art, butadiene acrylonitrile elastomers, (poly) isobutylene-co-isoprene, polyacrylates, polyesters, polyethers, fluoroelastomers, silicone elastomers, thermoplastic elastomers, ethylene copolymers. Particularly useful elastomers are block copolymers of conjugated dienes and vinyl aromatic monomers. Butadiene and isopropene are the preferred conjugated diene elastomers. Styrene, vinyltoluene, and t-butylstyrene are preferred conjugated aromatic monomers. Copolymers of blocks incorporating polyisoprene can be hydrogenated to produce thermoplastic elastomers having elastomeric saturated hydrocarbon segments. The polymers can be polymers of three simple blocks of type ABA, copolymers of multiple blocks of the type (AB) n (n = 2-10) or copolymers of radial configuration of the type R- (BA) x (X = 3-150 ), wherein A a block of a polyvinyl aromatic monomer and B is a block of a conjugated diene elastomer. Many of these polymers are commercially produced by the company Shell Chemical Co, and are described in the bulletin "Kraton Thermoplastic Rubber", SC-68-81. More preferably, the elastomeric material contains one or more of the elastomers mentioned above. The low modulus elastomeric material may also include fillers such as carbon black, silica, glass microballoons, etc., up to an amount not exceeding about 300% by weight of elastomer, preferably not exceeding about 100% by weight , and can be extended with oils and vulcanized with sulfur, peroxide, metal oxide or systems of radiation curing using well known methods by people with ordinary knowledge in the handling of rubber. Mixtures of different elastomeric materials can be used together or one or more of the elastomeric materials can be mixed with one or more thermoplastics. High density polyethylene, low density, and low linear density can be cross-linked to obtain a material with appropriate properties, either alone or as mixtures. The proportion (volumetric percentage) between the polymeric material and the fibers or fabrics varies according to rigidity, shape, heat resistance, wear resistance, combustion resistance and other desired properties. Other factors that affect these properties include the spatial density of the domain matrix, the percentage of gaps within the fibrous tissue, the randomness of the matrix islands, and other variables related to the placement, size, shape, positioning and composition of the matrix. the fibers and polymeric materials. A specific and preferred method for making the composite article of the present invention is illustrated in Figure 7. It is a method for making a composite article comprising a fibrous tissue wherein the fibers are oriented unidirectionally. The filaments 16 are wound on a polyethylene film 102 to form a fibrous fabric 12. An elastomer latex, thermoplastic elastomer or thermoplastic precursor for a domain matrix 14 is sprayed on the fibrous tissue 12. Once sprayed, the fibrous tissue 12 with domain matrix precursor 14 is fed to a furnace 50 to provide a bond between the fibrous tissue 12 and the domain matrix precursor 14. Once cooled, a unidirectional tape 52 is formed. Polymeric solutions can be employed in a similar manner . Thermosetting resins and monomers can be sprayed into the fibrous tissue 12 and subsequently reacted. Masks or templates can be used to control the pattern of domain matrices 14, as for example the use of a series of parallel wires to sift continuous lengths having a narrow width of less than 200 microns. In addition, the geometries used to create flexible structures through the use of 3 sets of parallel seams can be used, in accordance with that disclosed in U.S. Patent Nos. 5,316,820 and 5, 362,527, the disclosures of which are incorporated by reference. However, any method with any fibrous tissue can be employed. Alternatively, a polymeric latex can be applied to the fibrous tissue 12 and subsequently attached to the fibrous tissue 12 with heat and / or pressure. The fibrous tissue 12 can come into contact with pressure rollers 200 fed from latex containers 202, as shown in Figure 8. The fibrous tissue 12 passes into the constriction between the pressure rollers 200. The pressure rollers 200 fall into the containers 202 and the latex 208 adheres to the patterns, such as uninterrupted lines 204 or points 206, on the pressure rollers 200. As the unidirectional tape comes in contact with the latex coated patterns 208 of the rolls of pressure 200, the polymer is transferred into the fibrous tissue 12 to form matrix islands 18. The fibrous tissue 12, with the fixed matrix islands 18, can be heated, if desired. Limited amounts of polymer are collected in the fibrous tissue 12. The amounts are such that areas without polymer are formed in the fibrous tissue, or tape, and final product. In general, the amount of polymers is within a range of about 50% or less, preferably 20% or less, more preferably from about 20% to about 2%, preferably still greater than about 15% to about 5%. %, and especially 10% to about 5% of the surface area of the filaments 16 in the fibrous tissue 12. The discontinuous distribution of the matrix composition can be achieved by other means. For example, the present invention includes lamination of stitches of a fibrous fabric with at least one non-continuous layer of polymers. It can be applied by feeding the polymers in the first layer discontinuously or by using a perforated or patterned layer where there are areas without polymer and areas with polymer, ie, holes. The discontinuous polymeric layer can be laminated with the fibrous tissue under application of heat and pressure in order to obtain a discontinuous domain matrix in the fibrous tissue. This results in a fibrous tissue positioned positionally by the domain matrix such that discrete matrix islands are formed with empty areas therebetween. The composite article may contain from 2% resin by volume (matrix) distributed sufficiently to allow the fibrous tissue to maintain its integrity despite the high volumetric percentage of fiber or up to 50% of resin in volume distributed sufficiently to form gaps between the fibers. filaments of fibrous tissue. The matrix can be applied to the fibrous tissue in various ways, such as, for example, in a liquid manner, in the form of a sticky solid, or in suspended particles or as a fluidized bed. Alternatively, the matrix can be applied as a solution or emulsion in a suitable solvent that does not adversely affect the properties of the fibrous tissue. Suitable applications of the matrix include spraying printing, paste, powders by electrostatic methods and / or other suitable matrix applications, the type of application of a particular situation can be determined by those skilled in the art. While any liquid capable of dissolving or dispersing the matrix polymer can be employed, preferred groups of solvents include water, paraffin oils, ketones, alcohols, aromatic solvents, or hydrocarbon solvents including paraffin, toluene and octane oils. The techniques used to dissolve or disperse the matrix polymers in the solvents will be the techniques conventionally used for the coating of similar elastomeric materials in various substrates. Other techniques for the application of the polymer (matrix) on the fibers can be used, which include the high-mode precursor coating (gel fiber) before high-temperature drawing operations, either before or after solvent removal from the fiber. The fiber can then be stretched at elevated temperatures to produce the coated fibers. The gel fiber can be passed through a solution of the appropriate coating polymer (the solvent can be paraffin oil, aromatic or aliphatic solvent) under suitable conditions to achieve the desired coating. The crystallization of the high molecular weight polyethylene in the gel fiber may or may not have taken place before the fiber fabric passes into the cooling solution. The fibers and networks produced in this way are formed in composite materials as a precursor or fibrous tissue to prepare the composite articles. The low density fibrous webs of the present invention can be used to create consolidated panels that offer excellent ballistic protection. The term "composite article" is intended to include combinations of fibers or fabric with polymeric material in the form of matrix islands, which may include other materials such as fillers, lubricants or the like according to the above. Additional methods for fixing domain matrices 14 may include, without limitation hot melt, emulsion, paste, surface polymerization, entanglement of fibers, film interleaving, electrocoating and / or dry powder techniques. Composite materials can be constructed and arranged in various ways. It is convenient to characterize the geometries of such articles composed of the geometries of the fibers and then to indicate that the matrix material can occupy a part or all of the empty space left by the fiber network. One arrangement of this suitable type is a plurality of layers of laminates wherein the coated fibers are placed in a sheet-like assembly and are aligned parallel to each other along a common fiber direction. Successive layers of such unidirectional coated fibers can be rotated relative to the previous layer. An example of such laminated structures are composite articles with the second, third, fourth and fifth layers rotated plus 45 °, -45 °, 90 °, and 0 °, relative to the first layer, but not necessarily in this order. Other examples include composite articles with alternating layers rotated at 90 ° relative to each other, for example 0/90, + 45 / -45, + 30 / -60, etc. the present invention includes composite articles having several layers. They may contain from 1 to 500, preferably from 2 to 100 and especially from 2 to 75 layers. The normal technique for forming laminated products includes the steps of placing coated fibers in a desired network structure, and then consolidating and heating the overall structure to cause the coating material to flow and occupy a fraction of the void spaces, thereby producing a matrix keep going. Another technique is to place layers or other structures of coated or uncoated fiber adjacent to various forms, and between various forms, for example films, of the matrix material and then to consolidate and thermally harden the overall structure. In the above cases, it is possible that the matrix may become sticky or flow without complete fusion. In general, if the matrix material is heated only to a point of tackiness, higher pressure is generally required. Likewise, the pressure and time for hardening the composite article and for achieving optimum properties will generally depend on the nature of the matrix material (chemical composition as well as molecular weight) and the processing temperature. For the purposes of the present invention, a volume of empty substance (without matrix) must remain. Multiple tapes containing the compound 10 of the present invention can be combined together. The North American patents number 5, 061,545, and 5,093, 58 disclose various combinations of two-layer composite articles wherein the fibers in each layer are unidirectional fibers. The fibers of adjacent layers are disclosed at an angle of 45 ° to 90 ° between them, with an angle between fibers being preferred in adjacent layers of approximately 90 ° therebetween. Disclosures of U.S. Patent Nos. 5,061,545 and 5,093,158 are incorporated herein by reference. The composite articles of the present invention may possess an unusually high fiber content of 90 to 98% by volume and have improved ballistic effectiveness as compared to composite articles having a continuous polymeric matrix. In addition, if useful in commonly known articles designed to withstand a ballistic impact, such as bulletproof vests, helmets and body armor, the present invention is especially effective against explosives and / or impacts at very high speed of up to about 7 kilometers per second, and has utility in a space environment where ballistic impacts can occur with micrometeorites. Experimental Procedure Step A. Preparation of dry fiber fabrics A thread was wound on a rotating drum of a filament winder. The drum had a diameter of 76 cm (30 inches) a length of 122 centimeters (48 inches) and was covered with a film Halar®, a copolymer of chlorine, trifluoroethylene, and ethylene, a product made by AlliedSignal Specialty Films of Pottsville, Pennsylvania before rolling. 5.08 cm wide (2 inch) strips of double adhesive tape were applied parallel to the drum axis at intervals of 35.4 centimeters (10 inches) from center to center. The thread was wound on the ribbon. An adhesive tape to frame (coated) on one side was applied on the double adhesive tape covered with thread to ensure the maintenance in place of all the filaments. Halar® film covered with yarn was cut out from the drum and separated along the centerline of each tape. The result was the supply of 20.3 centimeters (8 inches) long dry parallel threads supported by a Halar® film and held in place by a tape measuring 2.45 centimeters (one inch) wide at both ends. B. Preparation of Experiment Protection Panels The 20.3 cm long (8 inch) sections from step A above were placed on a metal sheet and a tape was applied to hold the lead wires in place. A matrix resin was applied (see examples for more details) and a second section of 20.3 centimeters (8 inches) was placed over the first section of 20.03 centimeters (8 inches) that was rotated 90 ° in relation to the orientation of the fibers with the film Halar® above. An aluminum plate of 0.375 centimeters (1/8 inches), 19 cm x 19 cm (7.5 inches x 7.5 inches), was centered on the threads and the assembly was placed in a hydraulic press at a temperature of 120 ° C, force of 3 tons for 10 minutes. The metal plate acted as a spacer to separate the press plates from the ribbons surrounding the fiber fabrics. C. Measurement of the flexibility of the panels For the application of body armor, panels of the present invention should have a similar or greater flexibility to the structures of existing fabrics than conventional bullets. A simple test to determine a measure of flexibility is to place a square panel of a flat surface and allow one side to protrude on one edge (side of the panel parallel to the edge) by the length (1). The vertical distance (h) for the flat surface of the unsupported side of the panel is measured and the value of (h / 1) is calculated. When h / 1 equals l, the panel is extremely flexible, and when h / 1 equals 0, the panel is extremely rigid. To compare the flexibility of a panel with the flexibility of a control fabric, the percent flexibility is calculated as follows: 100% x (h / l) panel / (h / 1) fabric =% flexibility percentage for an armor body, it is desirable that the panels have a percent flexibility of from about 50% to about 150% of the woven fabric resistant to control bales without a matrix, preferably from 70% to about 150%, and most preferably from 85% to approximately 150%, in accordance with that described in example 10.10 below. Preferably, the h / 1 ratio is about 0.7 or more, more preferably about 0.85 or more. Example 1 Fibers of Spectra® 1000 (215 denier, 60 filaments per tip), commercially available from AlliedSignal Inc. of Petersburg, Virginia (40 tips per inch (EPI) and nominal surface density (AD) of 0.000376 gm / cm2), and a Kraton® rubber matrix resin, type G1650, granular, manufactured by Shell Chemical Co of Houston, Texas (the particles were passed through a 600 micrometer sieve number 30 or 0.0234 inches) were used in the experiment procedure presented above. The matrix resin was used with 7.5% by weight (total) dispersed in the bottom fabric before folding. After molding, the matrix resin became connecting islands of filament spots within the fiber strand and between the fiber strands. The panel was initially paper-like, but its flexibility resembled that of the fabric after bending and flexing. EXAMPLE 2 Example 1 was repeated with a matrix resin of 15% by weight. The results were the same as in Example 1. However, the panel was more robust and more resilient to delamination. Example 3 Example 1 was repeated with a matrix resin of 20% by weight and an additional layer of polyethylene film 0.000889 cm (0.00035 inch) thick, manufactured by Raven Industries of Sioux City, South Dakota was placed in the outer side of both fiber fabrics (the Halar® film was removed and separation paper was placed on the P film before pressing). The panel presented a robust structure with good flexibility.

Example 4 Fibers of Spectradr) 1000/215/60 (40 tips per inch (EPI) and nominal surface density (AD) of 0.00376 gm / cm2) and Prinlin B7137X-1 matrix resin, an aqueous dispersion of Kraton® D1107 rubber manufactured by Pierce & Stevens of Buffalo, New York, were used in the experimental procedure presented above. Both fiber fabrics were sprayed with small drops of Prinlin and dried before molding, providing 85% by weight of fibers. The panel was initially paper-type but its flexibility was similar to the flexibility of fabric after bending and bending. Example 5 Fibers of Spectra® 100/215/60 (15.7 tips per centimeter (40 tips per inch) (EPI) and nominal surface density (A) of 0.00376 gm / cm2) and a diluted matrix resin of 3 parts of water and A part of Prinlin B7137X-1 were employed in the experimental procedure mentioned above. Both fiber fabrics were sprayed with small fine drops of Prinlin and dried before molding, providing 95% by weight of fiber. The panel was initially paper-like, but its flexibility resembled that of a fabric after bending and bending. The panel was less robust than the example panel 4. Example 6 Spectra® fiber 1000/215/60 / 40 tips per inch (EPI) and nominal surface density (AD) of 0.00376 gm / cm2) and a matrix resin of S3DSBK polyethylene rotational molding powder, 120 microns (thin, manufactured by PFS Thermoplastic Powder Coatings Inc. of Big Spring, Texas, was used in the aforementioned experimental procedure) The PE was dusted into the upper fiber fabric before knowing the creases by shaking, and the estimated amount PE after molding was 14% by weight of the total weight.The panel was initially paper-type, but it became cloth-type with handling.A low friction surface was produced.Example 7 Spectra® 1000/215/60 (40 tips per inch (EOI) and nominal surface density (A) of 0.00376 gm / cm2) and a single polyethylene film, 0.000889 centimeters (0.00035 inches) thick, manufactured by Raven Industries, was placed between the two you of fibers to serve as a control for Example 6. The panel was less flexible than the panel of Example 6, but was considered useful. Example 8 Fibers of Spectra® 1000/215/60 (40 tips per inch (EPI) and nominal surface density (AD) of 0.00376 gm / cm¿) were used without matrix resin. After molding, the panel presented a paper-like quality and broke down when it was handled. Example 9 Fibers of Spectra® 1000/1300, 240 filaments per tip, an AlliedSignal Inc. product, (9.25 tips per inch (EPI) nominated surface density (AD) of 0.005266 gm / cm2) were sprayed with a matrix resin of Prinlin B7137X-1 and processed according to the experimental procedure mentioned above, with drying before molding, to provide 78% by weight of fiber. The panel was significantly more flexible than similar continuous fiber matrix products, which had an equivalent fiber surface density. Example 10 Examples 10.1-10.3: Thermoplastic elastomeric monofilaments were created by extruding a mixture of two thermoplastic elastomers (Kraton® G1652 and 1657) in the weight ratio of 2: 1. 650 and 1300 denier elastomeric fibers were formed into unidirectional tapes in the following manner: a Halar® film was placed in a drum with a two-sided tape of 5.08 centimeters wide (2 inches) fixed at 48.26 centimeters intervals (19). inches), from center to center, along the longitudinal direction. The thermoplastic elastomeric fibers were wound to provide 1.81 tips / cm (4.6 tips per inch) in width. A single-sided tape was fixed over the position of the two-sided tape to anchor the fiber tips in place. The anchor tapes were cut to the half providing fabrics with lengths of 43.18 centimeters (17 inches) of usable unidirectional fiber mat where the filaments are held together through rubber strips isolated. The fabrics were cut at 43.18 cm (17 inches) intervals along the longitudinal direction to produce 43.18 cm (17 inch) squares of unidirectional fiber mat having considerable spacing between the monofilaments. Unidirectional Spectra® fiber tapes were prepared in the same way, except that the 1300 denier Spectra® 1000 was rolled at 1.02 points per centimeter (2.6 points per inch) in the drum. Stabilized composite panels were prepared by cross-folding a rubber mat with a Spectra® tape and molding them together at a temperature of 100 ° C at a pressure of 1076 x 105 kg / m2 (10 tons per square foot). The stabilized panels were cross-folded, the Halar® film was removed and then the panels were molded together (same conditions as those used to build the stabilized unidirectional tape) with the resin-rich sides of the stabilized unidirectional tape facing each other . The results appear in the following table 1. Table 1 Comparative ballistic performance of flexible reinforcement in surface density of 1 kg / pr against lead bullets of 0.38 caliber - reinforcement with rubber crosslinker Matrix sample (kg / pr)% by weight of fibers # 10.1 (4.6 tips 1.04 81 / inch) (1.81 tips / cm) # 10.2 (2.3 tips 1.05 80 / inch) (0.91 point / c) # 10.3 (4.6 points 1.24 66 / inch) (1.81 tips / cm) Sample No of panels V50 (m / s) SEAT (Jm2 / kg) # 10.1 (4.6 tips 8 271 3770 / inches) (1.81 tips / cm) # 10.2 (2.3 tips 8 245 295 / inches) (0.91 tips / cm) # 10.3 (4.6 tips 8 244 247 / stitches) (1.81 tips / cm ) the comparison of 10.1 and 10.2 shows that the fiber lattice is more effective with the same weight percentage of elastomeric lattice. An additional elastomeric grid makes the panels rigid and less effective from a ballistic perspective (10,3). The results indicate that the weight percentage of the grid and the size must be optimized for optimal protection against a specific ballistic threat. 10.4: Comparative example: a comparative example of a parallel fiber fabric (a commercial product of AlliedSignal and sold under the trade name of Spectra Shield® single element, 1300 denier yarn of Spectra® 1000 fibers, 240 filaments per yarn) is coated with a D1107 solution of Kraton® in cyclohexane. It regularly covers the fabric of parallel fibers, which passes through a drying chamber to remove the solvent in order to produce a unidirectional tape material. This material is cross-folded and the entire polyethylene film is laminated on the lower surface and on the upper surface in order to prevent the panels from sticking together. The surface density of panel, fiber, matrix, and PE film were 0.147, 0.105, 0.0261, and 0.0157 kg / m2, respectively. The PE film had a melting point of 114 ° C. 10.5; A Halar® film, manufactured by AlliedSignal Specialty Films, was wrapped around a drum 121.92 centimeters (4 feet) long and 76.2 centimeters (30 inches) in diameter. The drum was rotated and a Spectra® 1000 fiber (1300 denier) was wrapped at 3.65 tips / cm (9.26 tips per inch) the fiber fabric was sprayed with a latex (Kraton® DI107; rosin in a weight ratio of 3: 1, Prinlin B7137X-1, a product of Pierce and Stevens). This unidirectional tape, along with the Halar® backing, was cut into 38.1 centimeters (15 inches) squares and folded 0/90 with latex at the bottom. The panel was then molded at a temperature of 125 ° C for 15 minutes at 1076 x 10 (5) kg / m2 (10 tons / square foot), providing 81% by weight of fiber. The Halar® film was removed and the polyethylene film (the same as the film used in Example 10.4) was placed on the outside of the 0/90 panel and the entire assembly was molded in accordance with the previously described, except that the Molding time was 2 minutes. 10.6: This sample was constructed to be similar to Example 10.5, except that a polyethylene film (identical to the film of the panels of Example 10.5) was wrapped in a metal drum of 121.92 centimeters (4 feet in length and 76.2 centimeters (30 inches) in diameter and a latex was sprayed on its surface in circular domains in elastomer having a bandwidth of 125 to 250 microns and covering approximately 25% of the film surface. sprayed with a Wagner Power Painter - Model 3 10 using a 0.8 mm nozzle Spraying started at one end of the rotating drum and proceeded to the other end, producing individual circular domains of Kraton D1107 Spectra 1000 Fiber was rolled in an identical manner as described in Example 10.5 A robust unidirectional tape was produced A series of 0/90 panels were molded which had the polyethylene fiber on the surface. The molding was carried out at a temperature of 80 ° C, 95 ° C, 105 ° C and 130 ° C for 15 minutes at 1076 x 10 (5) kg / m2 (10 tons / square foot). As the molding temperature increased, the panels became more paper-like and less cloth-like in their flexibility. A 0/90 panel was molded against a set of washers 0.91 centimeters thick (0.075 inches), external diameter 221 centimeters (0.37 inches) and internal diameter of 0.94 cm (0.37 inches). The shapes of the fully consolidated washers were printed on the panels. This demonstrated that consolidation patterns can be generated from panels of this invention. Useful domain structures can be constructed to provide easily bent continuous lines (such as sets of equilateral triangles). Eight panels molded at a temperature of 95 ° C, were designated as in example 10.6 and tested against 0.38 caliber lead bullets. In addition, a panel was placed in a dot junction mold having a square grid with a raised circular section at the grid intersections. The circular sections had a diameter of 1.0 mm and the distance from center to center was 7 mm. The panel was placed in a press at approximately 3450 kPa (500 psi) and molded for 150 seconds at a temperature of 115 ° C. The panel remained flexible. Clearly you can create several patterns through this molding technique. 10.7: This sample was created in the same way as in Example 10.6, except that a 1500 denier aramid figure, Twaron fiber (an Akzo product, 1450 denier yarn, 1.5 denier per filament, tensile strength) was wound. 24.4 g / denier, module: 8.05 g / denier) on the rotating drum, 3.16 points / cm (8.03 points per inch). Circular domains were created in the polyethylene film in a manner similar to those in Example 10.6. The domains created by spraying into the fiber fabric were also distorted in the same way as in Example 10.6. An electron scanning microscope indicated that the coated domains were discontinuous. The domains were much longer in the direction parallel to the length of the fibers (1), with dimensions varying from 150 micras to 500 micras in this direction. The L / D ratio presented a variation e 3 to 1 to 25 to 1 for these domains. . 8: Thermoplastic elastomeric fibers were created by extruding a mixture of Kraton® G1652 and 1657 in the weight ratio of 2: 1 unidirectional tapes made with elastomeric fibers (650 denier) were formed as follows: thermoplastic elastomeric monofilaments were created by extruding a mixture of two thermoplastic elastomers (Kraton® G1652 and 1657) in the weight ratio of 2: 1. 650 and 1300 denier elastomeric fibers were formed into unidirectional ribbons as follows: a Halar® film was placed on a drum with 5.8 centimeters wide (2 inches) tape on both sides fixed at 48.26 centimeters (19 inches) intervals ), from center to center, over the longitudinal direction. The thermoplastic elastomeric figures were coiled to provide 1.81 tips per centimeter (4.6 points per inch) in width). A single-sided tape was fixed over the position of the tape on both sides to anchor the fiber tips in place. The anchor tapes were cut in half to provide 43.18 cm (17 inch) lengths of a usable unidirectional fiber mat where the filaments are held together through insulated rubber strips. The fabrics were cut at 43.18 centimeters (17 inches) intervals along the longitudinal length to produce 43.18 centimeters (17 inches) squares of unidirectional rubber fiber mat having a considerable spacing between the monofilaments. Unidirectional Spectra® fiber tapes were prepared in the same manner, except that Spectra® 1000 fibers of 1300 denier were rolled at 1.02 spikes per centimeter (2.6 spikes per inch) onto the drum. Stabilized composite panels were prepared by cross-folding a rubber mat with a Spectra® tape and molding them together at a temperature of 100 ° C for 5 minutes under a pressure of 1076 x 103 kg / m2 10 tons per square foot). The stabilized panels are then folded crosswise, the Halar® film was removed, and then the panels were molded together under the same conditions as the conditions used to construct the stabilized unidirectional tape) with resin-rich sides of the unidirectional tape stabilized face to face. Unidirectional Spectra® fibers were prepared in the same manner except that Spectra® 1000 fibers of 1300 denier were rolled at a rate of 3.65 tips / cm (9.26 tips per inch) in the drum. Stabilized unidirectional tape panels were prepared by cross-folding rubber with a Spectra® panel and molding them together at a temperature of 100 ° C for 5 minutes under a pressure of 1076x10 (5) kg / m2 (10 tons per square foot) . These stabilized unidirectional tapes were cross-folded, the Halar® film was removed, and then the panels were molded together using the same conditions as those used to build the stabilized unidirectional tape with the resin-rich sides of the stabilized unidirectional tape facing among them . 10.9: Water vapor transmission The relative capacity to transmit water vapor through a panel of this invention (example 10.3) compared to a Spectra Shield® material was determined by placing 15 grams of water in a 56.7 jar. g (2 ounces) wide mouth (internal diameter 42 mm) and recording the weight loss in 24 hours at room temperature and under a relative humidity of 50%. The panels were fixed on the jars using an adhesive tape on both sides around the jars. A 1000 Spectra® ballistic fabric (style 955-215, denier, taffeta knit of 21.7 x 21.7 tips / cm (55x 55 tips / inches)) was also tested. The structures of the present invention clearly transmit the water vapor in regimes similar to the fabric. The data is shown in Table 2 below. Table 2 Comparison of water loss Shows loss in weight% of weight loss * Control - part 8.05 100 Open top Single element (example O.Olg 0.12 . 4) Reinforced with grid 16 20 (example 10.3) Spectra fabric 2.39g 30 * The percentage of weight loss is provided through the following formula: 100 x Ws / Wc, which are the weight loss for the sample under consideration and the weight loss of the open container, respectively. 10.10: Flexibility The comparison of the flexibility of the individual commercial element, the reinforced panel with example grid 10.3 and a commercially woven 1000 Spectra® fabric was made (flat fabric (215 denier to Spectra®) 1000 / 17.32 x 17.72 points / centimeter ( 45 x 45 tips / inch), a product of Clarks-Schwebel). The sample was placed on a flat surface and allowed to come out of the edge over a length (1) of 13 centimeters. The distance (h) from below of the flat surface of the free side was determined. The greater the distance (h), the more flexible the structure. As can be seen from Table 3, below, the non-woven panel with the reticle was still more flexible than a 1000 Spectra® woven ballistic fabric. The samples were flexed before the test to simulate a stress elimination. Table 3 Comparison of panels flexibility Sample length height h / 1% flexi¬ 81) (c) (h) (cm) bility Unique element 13 4 0.3077 36 Ballistic fabric 13 11.0 0.8462 100 Reinforced panel 13 11.5 0.8846 104 with grid Example 11 11.1: a Halar® film manufactured by AlliedSignal Specialty Films, was wrapped around a drum of 121. 92 centimeters (4 inches) long and 76.2 centimeters (30 inches) in diameter. 5.08 cm (2 inch wide) strips of adhesive tape on both sides were applied over the length of the drum at intervals of 20.32 centimeters (8 inches) .The drum was rotated and 1000 Spectra® fibers (1300 denier) were rolled at a rate of 3.65 tips per centimeter (9.26 tips per inch) After wrapping the 1000 Spectra © yarn, 5.08 cm (2 inch wide) strips of protective tape were applied over the areas covered by the adhesive tape on both sides to firmly anchor the fibers in place Adhesive tapes, together with the Halar® film and Spectra® fibers were cut through the center line of the adhesive tape to produce mats with fiber lengths of 20.32 centimeters (8 inches) ) and width of 121.92 centimeters (48 inches) .The mats were further cut to convenient sizes for use with elastomeric fibers.A mono elastomeric fiber Kraton® G1650 filament (2212 denier) was prepared by extruding the polymer through a 0.051 cm (0.02 inch) die at a temperature of 260 ° C using an Instron capillary rheometer. The parallel 20.32 cm (8 inch) square fiber fabric was adhered on a metal plate and an adhesive tape was placed on both sides on two sides of the fabric with a length of tape parallel to the longitudinal direction of the fibers. The Kraton® G1650 fibers were placed perpendicularly to the direction of the fibers and anchored on the tape on both sides of the fabric at 1 cm intervals. Robust unidirectional tapes were prepared by molding between metal plates with a Halar® film on one side and stirring it after molding at a low pressure 125 ° C in a hydraulic press. The tapes were cross-folded and molded again to create 0/90 panels with a total surface density of 0.154 kg / m "and 32% by weight of matrix The width of the deformed Kraton® G1650 fiber was approximately 3 mm. mm, which corresponds to a 49% surface coating, after a certain initial flexing, a soft low friction panel was created.At the molding process, distortion of the Spectra® fibers was observed, voids were removed, and initial stiffness was high, compared to the flexed material 11.2: this sample was identical to Example 11.1 except that the Kraton® fiber was cut into 3 cm segments that were randomly placed in the fiber fabric, which was then molded to produce a ribbon Unidirectional flow The Kraton® G1650 flow caused a significant distortion of the fiber fabric, an undesirable characteristic. 11.3: This sample was similar to Example 11.1 except that the elastomeric fiber was Kraton® G1651 of 275 denier that was extruded through a die of 0.007 inch at a temperature of 260 ° C. both the unidirectional tape and the folded panel so crossed 0/90 resulted in 5.5 wt.% matrix. The surface density of the 0/90 panel was 0.1113 kg / m2. The elastomeric fiber widened to less than 1 mm, which resulted in 20% of the panel area with elastomeric coating. 11. 4: This sample was similar to Example 11.1, except that Kraton® G1651 elastomeric fibers of 811 denier were oriented at 45 ° with respect to the longitudinal direction of the Spectra® fibers. The elastomeric fiber was extruded through a die of 0.0305 centimeters (0.012 inches) at a temperature of 260 ° C. both the unidirectional tape and the resulting 0/90 cross-folded panel exhibited 20 wt.% Matrix. 2 different structures were possible, the elastomeric fibers forming a rhombus shape with a series of lines parallel to 45 ° in relation to the lengths of the Spectra® fibers when the resin-rich sides were pressed together, the final molded panel was consistent and It had a very low friction. Example 12 Tapes were prepared as follows: a PE film, 0.000889 centimeter wide (0.00035 inch) manufactured by Raven Industries of Sioux City, South Dakota was placed in a drum; the drum was rotated and sprayed latex on the surface of the film forming a statically uniform dispersion of small droplets; a Spectra® 1000/650 denier fiber, 240 filaments per tip, was then rolled onto the drum; and the Spectra® fiber fabric was sprayed with the latex. These tapes were robust enough to be handled to prepare a final cross-folded panel suitable for applications in bulletproof vests. The unidirectional tapes were cross-folded (0/90) and molded in different conditions, the cross-folded panels generally presented a good combination of good flexibility and good ballistic performance. Cross-folded panels show that control of the amount of matrix, consolidation and distribution can be adequate with properties to focus on a particular use. 12.1: A parallel fiber fabric was coated regularly with a Kraton® D1107 solution in cyclohexane, and then passed through a drying chamber to remove the solvent in order to produce a unidirectional tape material. This material was cross-folded and a 0.000889 centimeter (0.00035 inch) thick polyethylene film was applied, manufactured by Raven Industries of Sioux City, South Dakota on the upper surface and the lower surface to prevent the panels from sticking together among them. The molding conditions were 120 ° C for 10 minutes. The surface densities of the panel, fiber, matrix, and PE film were 0.147, 0.105, 0.0262 and 0.0157 kg / m :, respectively. The PE film had a melting point of 114 ° C. the polyethylene film added weight and rigidity compared to the Kraton® D1107 matrix, alone. 12. 2: Matrix present as discrete thermoplastic domains A Halar® film a product of AlliedSignal Specialty Films, PA was wrapped around a drum (121.92 centimeters (4 feet) long and 76.2 centimeters (30 inches in diameter) the drum was rotated and rolled a 1000 Spectra® fiber (1300 denier), at a rate of 3.65 tips per centimeter (9.26 tips per inch) .The fiber fabric was sprayed with a latex (Kraton® D1107 and Prinlin D7137X-1, a product of Pierce and Stevens in a weight ratio of 3: 1.) This unidirectional tape, along with the Halar® backing, was cut into 38.1 cm (15 inch) squares and folded crosswise 0/90 with tape on the inside. Cross-folding was then molded at a temperature of 125 ° C for 15 minutes at 076X 10 (5) kg / 2 (ten tons per square foot) .The Halar® film was removed and a polyethylene film was placed (identical to the movie used in Example 12.1 on the outer surfaces of the 0/90 panel and the entire assembly was molded identically to the first molding, except that the molding time was 2 minutes. 8 square panels of 38.1 cm (15 inches) were stacked together, said panels were clamped and tested against a clay backing using lead bullets of caliber 0.28 158 grains). The V50 value was 251.2 m / s (824 ft / s). 12: 3 of Kraton® D1107 and Prinlin with PE film (matrix domains were sprayed) 8 panels,% by weight of fibers at 81% and ADT = 1.04 kg / m2. This sample was constructed in such a way that it was similar to Example 12.2, except that a polyethylene film (identical to the film on the surface of the panels of Example 12.2) was wrapped in a metal drum 121.92 cm (4 feet) in length and 76.2 cm (30 inches) in diameter) and a latex was sprayed on its surface (Kraton® / Prinlin matrix surface density sprayed on the surface was 0.019 kg / m.). Circular elastomer domains within the plane of the Tape in the size range from 125 to 250 microns and coating of approximately 25% of the surface of the film were created.The spray process was performed with a Wagner Power Painter - Model 310 using a 0.8 mm nozzle. started at one end of the rotating drum and proceeded to the other end, producing individual circular matrix domains Spectra © Fiber 1000 was wound in an identical manner to that described in Example 12.2 and the fiber mat ras was also sprayed in a manner similar to example 12.2. This produced a robust unidirectional tape with the elimination of a release backup. A series of 0/90 panels were molded with the polyethylene film on the surface. The molding was carried out at a temperature of 80 ° C, 95 ° C, 105 ° C and 130 ° C for 15 minutes at 1076 x 105 kg / m2 (10 tons / square foot). As the molding temperature was raised, the panels became more paper-like and less similar to the fabric in terms of flexibility. The panel molded at 95 ° C was flexed a few times and its flexibility was measured in the manner described in Example 10.10. The panel presented a flexibility of 0.96 and a percentage flexibility of 114% compared to the ballistic fabric (see example 10:10). A 0/90 panel was molded against a set of washers (thickness: 0.19 cm (0.075 inch), external diameter: 2.21 cm (0.87 inch) and internal diameter: 0.79 cm (0.37 inch)). Fully bonded washer forms were printed on the panel. This demonstrated that consolidation patterns could be generated from panels of this invention. Useful domain structures, which provide continuous lines that can be easily bent (such as equilateral triangular sets), can be easily constructed. Eight of the panels molded at a temperature of 95 ° C were tested against .38 caliber lead bullets. In addition, one panel was placed in a spot-junction mold having a square grid with high circular domains at grid intersections (circular sections of 1.0 mm diameter and center-to-center distance of 7 mm). The panel was placed in a press at approximately 3450 kPa (500 psi) and molded for 150 seconds at a temperature of 115 ° C. The circular domains were consolidated (approximately 1.6% surface) and the remaining areas remained unconsolidated. The panel remained flexible. 12.4: This sample was prepared in accordance with what is described in Example 12.3. Table 4 Comparative ballistic performance of flexible armor against .38 caliber lead bullets shows ADT fiber% V50 (ft / s) SEAT domains (kg / m2 in weight [m / s] (Jm / kg) 12.1 1.05 72 720 [219.5 ] 234 No 12.2 1.04 81 824 [251.2] 310 Yes 1 122..33 1 1..2244 81 789 [240.5] 296 Yes 12.4 1.04 78 858 [261.5] 327 Yes Example 13 The following structures were investigated: A. A material Single-element Spectra Shield® This structure, which incorporates 0/90 prepeg, requires a PE film on the back and on the bottom to prevent panel fusion due to the matrix's stickiness (Kraton® D1107). The panels are coherent and have a relatively low fiber weight percentage (72%). The sandwich type construction prevents flexibility, as shown in table 5. B. Minor modification of the single element for improved performance The basic idea is to replace the matrix domains with a continuous matrix array in the commercial product of A in order to achieve greater flexibility. This was effected by spraying a Kraton® D1107 latex through a paint sprayer on a fiber fabric in a rotating drum, providing a statistically uniform distribution. The process was quite direct, providing domains on the surface of the fiber mat. Resin-rich surfaces were matched and the PE film was placed on top and bottom. The assembly was molded to produce flexible panels that were stacked to form ballistic targets, providing 81% by weight of fibers. With reference to table 5, it should be noted that ballistic efficiency (SEAT) is approximately 1.3 times greater than the ballistic efficiency of the commercial control (A), and that the percentage by weight of fibers is substantially higher than in the case of the commercial product. C. PE-Powder matrix designed for rotary molding The best ballistic results were achieved with that system. A linear low density polyethylene powder (Tm = 105 ° C) was pumped as a basket on a fiber mat in a rotating drum. The 0/90 panel made from this material was flexible and exhibited low surface friction. The advantages of PE powders were their lower cost and manufacturing processes without solvents. With reference to table 5, the ballistic performance (SEAT) was outstanding compared to the control sample A. D (l) -D (2). EPDM matrix / PE powder in a 1: 4 weight ratio Some difficulties were encountered in making parallel fiber fabrics with PE powder since the powder did not adhere to the fiber in the drum and had a tendency to fall. It was found that a PE powder paste in an EPDM solution exhibited good adhesion to the fiber mat in the rotating drum. However, the ballistic performance was not as good as in the case of the PE powder used alone. Table 5 presents a summary of the ballistic efficiency of these experimental materials, based on SEAT values. Table 5 Flexible ballistic armor Comparative Performance against caliber lead bullets ADT fiber sample 38% V50 (ft / s) SEAT domains weight [m / s] (JmVkg) A (control) 1.05 72 720 [219.5] 234 No B 1.04 81 824 [251.2] 310 If c 0. 981 88 854 [260.3] 353 If D (1) 1. 00 85 774 [235.9] 283 Yes D (2) 1. 04 80 750 [228.6] 257 Si Example 14 A flexible white reinforced with aramid fibers was prepared in accordance with that described in example 12.3. The Twaron fiber (an Akzo product, 1450 denier yarn, 1.5 denier per filament, tensile strength 24.4 g / denier, modulus: 805 g / denier) was replaced by the Spectra® 1000 yarn and wound on the drum ratio of 3.27 turns per centimeter (8.3 turns per inch). The target, which has seven 0/90 panels with ADT = 0.995 kg / m2, was ballistically tested against a .38 caliber lead bullet. V50 was 281.6 m / s (924 ft / s) and SEAT was 408 J-Kg / m2. The structure provided good ballistic protection. Example 15 15: 1: A Halar® film (a product of AlliedSigr.al Specialty Films, Pottsville, PA) is rolled around a drum, 121.92 cm long (4 feet) by 76.2 cm in diameter (30 inches). The drum was rotated and the PBZO fiber (1300 denier) was rolled at a rate of 3.65 points per centimeter (9.26 tips per inch). The fiber fabric is sprayed with a latex (Kraton® D1107 and Prinlin B7137X-1, a Pierce and Stevens product in a 3: 1 weight ratio). This unidirectional circuit, along with the Halar® backing, is cut into 38.1 centimeters (15 inches) squares and folded 0/90 with tape on the inside. The cross-bent material is then molded at a temperature of 125 ° C for 15 minutes and 1076 x 10 = kg / m "(10 tons / square foot) .The Halar® film is removed and a polyethylene film is placed on the the outer surfaces of 0/90 panel and the entire assembly is molded. Eight square panels 38.1 centimeters (15 inches) are stacked together, clamped and tested against a clay backing using bales of lead .38 (158 grains). The V50 value is expected to be higher than a similar amount of PBZO fiber in a conventional Shield-style product Example 16.1.1: A Halar® film (a product of AlliedSignal Specialty Films, Pottsville, PA) is wrapped around a drum , 121.92 cm long (4 feet) by 76.2 cm diameter (30 inches). The drum was rotated and PBZT (1300 denier) fiber was wound at a rate of 3.65 ends / centimeter (9.26 ends per inch). The fabric fiber is dew with a latex (Kraton © D1107 and Prinlin B7137X-1, a product of Pierce and Stevens in a 3: 1 weight ratio). This unidirectional tape, along with the Halar® backing is cut into 38.1 centimeters (15 inches) squares and folded 0/90 with tape on the inside. The cross-folded material is then molded at a temperature of 125 ° C for 15 minutes and 1076 x 105 kg / m2 (10 tons / square foot). The film Halar © is removed and a polyethylene film is placed on the outer surfaces of the 0/90 panel and the entire assembly is molded. Eight 38.1 centimeter (15 inch) square panels are stacked together, clamped and tested against a clay backing using .38 caliber lead balls (158 grains). It is expected that the V50 value is greater than a similar amount of PBZT fiber in a conventional Shield style product. The summary, description, examples and previous drawings of the present invention are not intended to limit said invention but are offered only as examples of the features of the invention that are defined in the claims.

Claims (20)

1. CLAIMS A composite article comprising several filaments and several matrix islands, each of said matrix islands connects at least two filaments, characterized in that each of said matrix islands has an average size of less than about 5 mm and said matrix islands together maintain the various filaments in a unitary structure.
2. The composite article according to claim 1, wherein the various filaments are arranged in a flat, essentially parallel assembly.
3. The composite article according to claim 1, wherein the plural filaments comprise individual filaments having an average modulus of about 300 g / denier or more and an average tenacity of about 7 g / denier or more.
4. The composite article according to claim 1, wherein the volumetric ratio between the matrix islands and the various filaments is about 0.4 or less.
5. The composite article according to claim 4, wherein the volumetric ratio between the matrix islands and the various filaments is from about 0.25 to about 0.02.
6. The composite article according to claim 5, wherein the volumetric ratio between the matrix islands and the various filaments is from about 0.2 to about 0.05.
7. The composite article according to claim 1, wherein the filaments are filaments selected from the group consisting of ultra high molecular weight polyethylene, ultra high molecular weight polypropylene, aramid, polyvinyl alcohol, polyacrylonitrile, polybenzoxazole, polybenzothiazole, glass, ceramics and combinations thereof.
8. The composite article according to claim 7, wherein the various filaments comprise ultra high molecular weight polyethylene.
9. The composite article according to claim 8, wherein the ultra high molecular weight polyethylene filament has a tenacity of about 30 g / denier or more and a modulus of about 1500 g / denier or more.
10. The composite article according to claim 7, wherein the various filaments comprise aramid.
11. The composite article according to claim 1, wherein the matrix islands comprise a flexible composition selected from the group consisting of elastomers, thermoplastic elastomers, thermoplastics, thermosetting, and combinations thereof.
12. 12. The composite article according to claim 11, wherein the matrix islands comprise an elastomer.
13. The composite article according to claim 10, wherein the elastic matrix islands comprise a combination of two or more elastomers, thermoplastic elastomers and thermoplastics.
14. 14. The composite article according to claim 1, wherein the domain matrix provides a robust filament structure.
15. 15. The composite article according to claim 1, wherein each filament within the composite article is in contact with at least one matrix island.
16. 16. The composite article according to claim 15, comprising several matrix islands in a predetermined pattern.
17. 17. The composite article according to claim 1, wherein said filaments are arranged in parallel in one direction.
18. 18. The composite article according to claim 1, wherein the average size of the matrix islands is less than 3 mm in a planar dimension.
19. 19. The composite article according to claim 1, wherein the average size of the matrix islands is less than 1 mm in a planar dimension.
20. 20. The composite article according to claim 1, wherein the composite article possesses at least 70% of the flexibility of a flat woven fabric made from Spectra® 1000/45 x 45 tips by 2.54 centimeters (inch). The composite article according to claim 1, wherein the composite article has a flexibility of about 0.7 or more. 2. The composite article according to claim 1, wherein the composite article has a flexibility of about 0.85 or more.