A ballistic material comprising high strength polyethylene fibers

Abstract: A ballistic material comprising high strength polyethylene fibers in which the fiber is characterized in that: it contains a high molecular weight polyethylene consisting essentially of a repeating unit of ethylene; it has an intrinsic viscosity number of 5 or larger and an average strength of 22 cN/dtex or higher; and the measurement of the fiber by differential scanning calorimetry (DSC) exhibits a temperature-increasing DCS curve having at least one endothermic peak over a temperature region of 140°C to 148°C (on the low temperature side) and at least one endothermic peak over a temperature region of 148°C or higher (on the high temperature side) or the number of frictions until the fiber is broken in an abrasion test according to method B for measuring abrasion resistance in the Testing Methods for Spun Yarn (JIS L 1095) is 100,000 or larger.

Description: The present invention relates to a ballistic material comprising novel high strength polyethylene fibers. More particularly, it relates to a ballistic material comprising high strength polyethylene fibers which can be widely used for industrial or private use. For high strength polyethylene fibers, there have been disclosed, for example, in JP-B 60-47922, high strength, high modulus fibers produced by the "gel spinning method" using ultrahigh molecular weight polyethylene as the base material. These high strength polyethylene fibers have already been widely used in various fields for industry, for example, as the ropes or nets for industrial or private use; as high performance textiles such as ballistic materials or items, or protective gloves; or as the geo-textiles or working nets in the filed of civil engineering and architecture. In recent years, these high strength polyethylene fibers have been required to have further improved performance, particularly durability, for example, mechanical durability over a long period or adaptability under severe conditions in use. Even textiles such as sportswears, or fishing lines have also been required to have durability when used for a long period. In addition, reinforcing sheets or strands to provide earthquake resistance have been required to have durability, particularly flexural fatigue resistance or abrasion resistance, such that when wound around pillars or other parts they cause no occurrence of fiber breaking at the corners. The high strength polyethylene fibers have excellent tensile strength and excellent Young's modulus indeed, but on the other hand, the structure of their highly-oriented molecular chains is responsible for the drawback that they have poor durability, particularly poor flexural fatigue resistance and poor abrasion resistance, for example, as compared with polyesters or nylons for ordinary garments. Such drawback has become some obstacle to the wide application of high strength polyethylene fibers in various fields for industry. Further, many attempts have been made to use high strength polyethylene fibers in the chemical processes, for example, application to non-woven fabrics such as chemical filters or battery cell separators, because of their excellent resistance to chemicals, light and weather or to apply high strength polyethylene fibers to reinforcing fibers for concrete or cement, because there has been a demand for fiber reinforced concrete products having high crack resistance and high toughness, as well as excellent impact resistance and excellent long-term durability, since accidents were caused by wall materials coming off or falling from the surface of railroad tunnels or bridges. However, when chopped fibers or staples are produced by cutting the conventional high strength polyethylene fibers, fibrillation of the fibers or their high surface hardness is responsible for the drawback that these fibers get stuck together by pressure to form a bundle of fibers, lacking in dispersibility. Further, when they are used as the reinforcing fibers for concrete or cement, their dispersibility in the cement matrix becomes deteriorated by flexure or entanglement of the fibers. For this reason, various treatments have been needed, for example, premixing with cement, hydrophilicity-providing treatment using metal oxides, or binding with resins. To overcome such drawbacks, the orientation of the extended polyethylene molecular chains should be more relaxed, which method, however, causes a lowering of strength and Young's modulus and cannot, therefore, be employed. Further, polyethylene fibers have no strong interaction between the molecular chains and easily cause fibrillation by repeated fatigue, which makes it very difficult to improve the durability of these fibers. Thus, an object of the present invention is to provide a ballistic material comprising high strength polyethylene fibers which fibers have about the same or higher strength and Young's modulus than those of the conventional high strength polyethylene fibers, and further have excellent flexural fatigue resistance and excellent abrasion resistance, and hardly cause fibrillation, and still further have high surface hardness. That is, the present invention relates to a ballistic material comprising high strength polyethylene fibers characterized in that: the fiber comprises a high molecular weight polyethylene consisting essentially of a repeating unit of ethylene; it has an intrinsic viscosity number of 5 or larger and an average strength of 22 cN/dtex or higher; and the measurement of the fiber by differential scanning calorimetry (DSC) exhibits a temperature-increasing DCS curve having at least one endothermic peak over a temperature region of 140°C to 148°C (on the low temperature side) and at least one endothermic peak over a temperature region of 148°C or higher (on the high temperature side). The present invention further relates to a ballistic material comprising high strength polyethylene fibers characterized in that: the fiber comprises a high molecular weight polyethylene consisting essentially of a repeating unit of ethylene; it has an intrinsic viscosity number of 5 or larger and an average strength of 22 cN/dtex or higher; and the number of frictions until the fiber is broken in an abrasion test according to method B for measuring abrasion resistance in the Testing Methods for Spun Yarn (JIS L 1095) is 100,000 or larger. Figure 1 shows a temperature-increasing DSC curve obtained by differential scanning calorimetry (DSC) of the high strength polyethylene fiber of Example 1. Figure 2 shows a temperature-increasing DSC curve obtained by differential scanning calorimetry (DSC) of the high strength polyethylene fiber of Example 2. Figure 3 shows a temperature-increasing DSC curve obtained by differential scanning calorimetry (DSC) of the high strength polyethylene fiber of Example 3. Figure 4 shows a temperature-increasing DSC curve obtained by differential scanning calorimetry (DSC) of the high strength polyethylene fiber of Comparative Example 1. Figure 5 shows a temperature-increasing DSC curve obtained by differential scanning calorimetry (DSC) of the high strength polyethylene fiber of Comparative Example 2. The high strength polyethylene fibers used for the ballistic material of the present invention (hereinafter the term "high strength polyethylene fibers of the present invention" should always be understood as meaning "high strength polyethylene fibers used for the ballistic material of the present invention") are composed of a high molecular weight polyethylene consisting essentially of a repeating unit of ethylene. As used herein, the expression "high molecular weight polyethylene consisting essentially of a repeating unit of ethylene" refers to a polyethylene, which may be regarded essentially as an ethylene homopolymer containing a repeating unit of ethylene at a ratio of 99.5 mol% or higher, preferably 99.8 mol% or higher, and which has an intrinsic viscosity number of 5 or larger, preferably 8 or larger, and more preferably 10 or larger. For the purpose of increasing the rate of polymerization, or the purpose of improving the creep and other characteristics of finally obtained fibers, the introduction of branches into the polyethylene by the addition of copolymerizable monomers such as α-olefins in very small amounts is recommended; however, higher amounts of copolymerizable monomers are not preferred for improving the durability of fibers because it is, for example, presumed that copolymerization with α-olefins prevents mutual sliding between the molecular chains in the crystals, which makes it impossible to achieve the relaxation of stress for continuously repeated deformation. If the base polymer has an intrinsic viscosity number of smaller than 5, it is difficult to exhibit the mechanical characteristics of fibers, particularly tensile strength. On the other hand, there is no upper limit to the intrinsic viscosity number; however, taking into consideration the stability and productivity in the yarn making process, the durability of fibers, and other factors, it is preferred that the intrinsic viscosity number is 30 or smaller. Intrinsic viscosity numbers larger than 30 may cause, for example, the lowering of durability in some cases depending upon drawing conditions for spun yarns. Thus the high strength polyethylene fibers of the present invention composed of a high molecular weight polyethylene consisting essentially of a repeating unit of ethylene come to have an intrinsic viscosity number of 5 or larger. As used herein, the intrinsic viscosity number of fibers refers to a corresponding value obtained by viscosity measurement in decalin at 135°C and extrapolation of η sp / c (where η sp is specific viscosity and c is concentration) toward zero concentration. In actual cases, viscosity measurement is carried out for some concentrations, and a straight line is drawn on the plot of specific viscosity η sp against concentration c by the method of least squares and extrapolated toward zero concentration to determine an intrinsic viscosity number. Further, the high molecular weight polyethylene as the base polymer is not particularly limited, so long as finally obtained fibers meet the above intrinsic viscosity number. For improving the durability of fibers to its limit, the use of a base polymer having more narrow molecular weight distribution is preferred. The use of a base polymer having a molecular weight distribution index (Mw/Mn) of 5 or lower, which polymer is obtained using polymerization catalysts such as metallocene catalysts, is more preferred. The high strength polyethylene fibers of the present invention have an average strength of 22 cN/dtex or higher. As used herein, the average strength refers to an average value of strength (cN/dtex) obtained by drawing of a strain-stress curve using a tensile tester under the conditions: length of specimen, 200 mm (gap distance between chucks); elongation rate, 100%/min.; atmospheric temperature, 20°C; and relative humidity, 65%; and calculation from the stress at the breaking point on the curve obtained (number of measurements, 10). For the high strength polyethylene fibers of the present invention, their measurement by differential scanning calorimetry (DSC) exhibits a temperature-increasing DCS curve having at least one endothermic peak over a temperature region of 140°C to 148°C (on the low temperature side) and at least one endothermic peak over a temperature region of 148°C or higher (on the high temperature side). The temperature-increasing DSC curve is obtained by using a specimen of fibers, which have been cut in 5 mm or shorter length, keeping the specimen in a completely free state under an atmosphere of an inert gas, and heating the specimen from room temperature up to 200°C at a heating rate of 10°C/min. For the endothermic peaks, only employed are peaks, of which peak temperatures can be read, and the increased DSC curve obtained is corrected for the base line, followed by reading of peak temperatures and peak heights. As used herein, the base line refers to the part of a DSC curve in the temperature region where no transition nor reaction occurs in the test specimen as defined in the Testing Methods for Transition Temperatures of Plastics (JIS K 7121). The peak height refers to the distance measured vertically to the axis of abscissa between an interposed base line and the peak crest. In the Testing Methods for Transition Temperatures of Plastics (JIS K 7121), the peak is defined as the part of a DSC curve where the curve leaves the base line and then returns to the same base line. In the present invention, when the temperature-increasing DSC curve obtained is differentiated ( i . e ., the first derivative curve is drawn) and the value of derivative ( i . e ., the distance measured vertically to the axis of abscissa between the first derivative curve and the axis of abscissa; the value of derivative has a plus or minus sign, if the curve is above or below the axis of abscissa, respectively) changes its sign from plus to minus, such part of the curve is defined as a peak, and the part of the curve where the value of derivative changes from the monotonous increase to the monotonous decrease while keeping its plus or minus sign is defined as a shoulder. From this definition, for example, it follows that the DSC curve shown in Figure 2 has two peaks and the DSC curve shown in Figure 4 has one peak and one shoulder. By the way, JP-A 63-275708 discloses high strength polyethylene fibers obtained by a special technique using copolymerization with α-olefins, and describes that when these fibers are wound around an aluminum pan to stand in a constrained condition under tension and then subjected to measurement by differential scanning calorimetry (DSC), two or more peaks arising from copolymerization, in addition to the main peak, are observed on the high temperature side. It is, however, well known that when high strength polyethylene fibers in such a constrained condition under tension are subjected to DSC measurement, it usually causes an increase of the melting point, or in some case, the occurrence of two or more peaks arising from crystal transition or other factors: In contrast, the high strength polyethylene fibers of the present invention are composed of a polyethylene which can be regarded essentially as an ethylene homopolymer, and the measurement by differential scanning calorimetry (DSC) in the present invention is carried out by using a specimen of fibers, which have been cut in 5 mm or shorter length, and keeping the specimen in a completely free state. To the inventors' knowledge, no report has been made in the past about high strength polyethylene fibers exhibiting, even in such case, two or more endothermic peaks on the high temperature side. The reason for the occurrence of two or more endothermic peaks on the high temperature side even in such completely free state seems to be the presence of a high-temperature melting-type crystal structure (hereinafter referred to as "HMC") different from the ordinary polyethylene crystal (hereinafter referred to as "EC"). As shown in Examples, favorable results are obtained when structure formation is achieved by more positive removal of solvents contained in the fiber surface. It can therefore be presumed that HMC is preferably formed on the surface layer of fibers, which HMC layer has a function to keep the strength of fibers and is a factor in the expression of extremely excellent flexural fatigue resistance and extremely excellent abrasion resistance. It is also presumed that excellent abrasion resistance prevents fibrillation and forms the fiber surface with high hardness. JP-A 61-289111 discloses semi-stretched yarns obtained by the spinning method using two kinds of special solvents and describes that their DSC curves drawn by measurement in a "free state" has two or more endothermic peaks. Although there is no other way but to guess what is this "free state", it is well known that two or more endothermic peaks may often be observed even when fibers, which have not been cut short, are inserted in an aluminum pan for measurement because although it can be said that these fibers are in a freer state than that in the ordinary measurement with fibers wound around a small piece of aluminum, the fibers in the pan are, in fact, partly fixed between the bottom and the cover of the pan or there occurs uneven distribution of stress over the specimen. To avoid such. influence in the measurement, a specimen should carefully be cut in very short length as done by the present inventors. Even if the measurement disclosed in the above publication is the same as that of the present invention, the temperature region of endothermic peaks disclosed in the above publication is different from that of the present invention, it is presumed from the following reason that the stretched yarns disclosed therein have poor flexural fatigue resistance and poor abrasion resistance. In the meantime, with the producing method disclosed in the above publication, i . e ., slow technique in which the first and the second solvents are substantially removed just after spinning, it is quite difficult to provide the fiber surface with a close structure. As described above, for the high strength polyethylene fibers of the present invention,' the temperature-increasing DSC curve thereof has at least one endothermic peak over a temperature region of 140°C to 148°C. In particular, such peak is preferably the main peak corresponding to the largest value of heat flow among two or more endothermic peaks found in the temperature-increasing DSC curve. It is presumed that the main peak reflects the ordinary structure (EC) occupying the major part of fibers, and if the peak temperature thereof is lower than 140°C, the fibers have insufficient heat resistance. In contrast, if the peak temperature thereof is higher than 148°C, the ordinary fiber structure becomes highly restricted, for example, an aggregate of completely-extended chains, lowering the durability of fibers. The present inventors have found that the durability of fibers, particularly flexural fatigue resistance in this case, becomes optimum when the main peak appears over a temperature region of 140°C to 148°C. For the high strength polyethylene fibers of the present invention, the temperature-increasing DSC curve thereof further has at least one endothermic peak over a temperature region of 148°C or higher (on the high temperature side). It is presumed that this endothermic peak on the high temperature side corresponds to the HMC structure having great influence on durability, particularly abrasion resistance, of which formation mechanism will be described below; and fibers exhibiting no endothermic peak on the high temperature side have extremely deteriorated abrasion resistance. As described above, it is presumed that the maximum endothermic peak on the high temperature side among two or more endothermic peaks found in the temperature-increasing DSC curves of the high strength polyethylene fibers of the present invention is derived from the HMC structure. Adjusting the height of this maximum endothermic peak on the high temperature side makes it possible to obtain high strength polyethylene fibers having optimum durability. In general, the fatigue of molecular-oriented fibers, of which typical examples are high strength polyethylene fibers, from flexure or abrasion is mainly caused by the fibrillation of the fibers from the surface layer. It is presumed that the high strength polyethylene fibers of the present invention have the surface layer of HMC with more entangled molecular chains, which results in a structure hardly causing fibrillation; therefore, the closer surface structure renders the fibers excellent flexural fatigue resistant and abrasion resistant, preventing the fibers from getting stuck together by pressure when they are cut. It is, however, important that the high strength polyethylene fibers of the present invention should have a particular ratio of HMC occupying the whole crystal structure. As described above, it is presumed that the maximum endothermic peak on the high temperature side is derived from the fusion of EC and the maximum endothermic peak on the low temperature side is derived from the fusion of HMC. The height ratio of these maximum endothermic peaks over the respective temperature regions is usually in the range of 1.4 : 1.0 to 3.0 : 1.0, preferably 1.5 : 1.0 to 2.9 : 1.0, and more preferably 1.6 : 1.0 to 2.8 : 1.0. If the ratio is lower than 1.4 : 1.0, i . e ., if the maximum endothermic peak on the high temperature side is relatively higher, this means that the ratio of HMC forming the surface layer of fibers is higher, which lowers the durability of fibers. This is probably because an excessive increase in the surface hardness promotes deterioration such as buckling fatigue. In contrast, if the ratio is higher than 3.0 : 1.0, i . e ., if the maximum endothermic peak on the high temperature side is relatively lower, the ratio of HMC is lower, which makes no trouble for strength or Young's modulus but also makes no improvement in durability, so that fibers cannot be prevented from getting stuck together by pressure when they are cut, making is impossible to obtain chopped fibers having good dispersibility. Further, the surface HMC structure according to the present invention is very effective for the improvement of impact resistance. To obtain high impact resistance, fibers are required to have high strength and high degree of elongation in the deformation at high strain rate, what is called, toughness. The surface HMC structure according to the present invention has a function to improve both of these characteristics. From the viewpoint of viscoelastic properties, polymer materials may be considered a combination of elastic components and viscous components as explained by, what is called, the Takayanagi model. In case of deformation at high strain rate, viscosity characteristics have a great contribution, and the surface HMC structure according to the present invention exhibits response on high strain deformation in the viscosity characteristics, making it possible to improve impact resistance. Therefore, the high strength polyethylene fibers of the present invention having such improved impact resistance are suitable for ballistic materials or items, or as the reinforcing fibers of helmets. Thus the high strength polyethylene fibers of the present invention have remarkably improved durability, particularly abrasion resistance, as compared with the conventional high strength polyethylene fibers. More specifically, the number of frictions until the fiber is broken in an abrasion test according to method B for measuring abrasion resistance in the Testing Methods for Spun Yarn (JIS L 1095) is 100,000 or larger. The high strength polyethylene fibers of the present invention should be produced with deliberation by a novel method of production, for example, the method described below, which is recommended, but it is, of course, not limited thereto. First of all, a high molecular weight polyethylene as described above is uniformly dissolved in a solvent to give a spinning solution. The spinning solution has a concentration of usually 50% or lower, preferably 30% or lower. The solvent may include volatile solvents such as decalin or tetralin and non-volatile solvents such as paraffin oil or paraffin wax. The use of volatile solvents is preferred. This is because for solvents which are in solid state or nonvolatile at ordinary temperature, the rate of solvent extraction from filaments is slow and it is, therefore, difficult to achieve sufficient formation of HMC, whereas volatile solvents in the fiber surface are positively evaporated in the spinning to give a higher concentration in the fiber surface, making it possible to form a specific crystal structure (HMC) in which molecular chains are more highly oriented and connected with each other. In case of conventional spinning techniques, a structural difference between the fiber surface and the inside is responsible for a decrease in the strength of fibers; the selection of spinning conditions to make the sectional structure of fibers as uniform as possible is, therefore, common knowledge for persons of ordinary skill in the art of not only gel spinning but also dry spinning, wet spinning, and melt spinning of polyvinyl alcohol and polyacrylonitrile, for example, i . e ., in the art of spinning in general. On the contrary, the present inventors have found that the formation of a structural difference between the fiber surface and the inside at the step of spinning, more specifically the formation of HMC by instant and positive removal of solvents in the fiber surface to thereby concentrate the tension of spinning on the surface layer, makes it possible to obtain fibers keeping high strength and high Young's modulus and further having excellent flexural fatigue resistance and excellent abrasion resistance. In the production of the high strength polyethylene fibers of the present invention, there is recommended a technique of blowing a high-temperature inert gas onto the discharged filaments just below the spinneret for the positive removal of solvents on the surface of the filaments. This results in the formation of a very thin HMC layer on the surface to thereby concentrate the tension of spinning, making it possible to form a specific structure in which molecular chains are connected with each other as described above. The temperature of the inert gas is usually 60°C or higher, preferably 80°C or higher, and more preferably 100°C or higher but below 150°C. For the inert gas, the use of a nitrogen gas is preferred from an economical point of view, but it is not limited thereto. The unstretched filaments thus obtained are heated again to remove the remaining solvents, during which they are drawn at a ratio of several times. Depending on the situation, multi-step drawing may be employed. The HMC structure of the surface layer formed in the spinning can never be eliminated in the later drawing steps, making it possible to obtain high strength polyethylene fibers having extremely excellent characteristics as described above. The high strength polyethylene fibers obtained, even if cut, hardly get stuck together by pressure when they are cut because of their having a close structure in the surface, although such sticking phenomenon is observed in the conventional fibers; therefore, chopped fibers or staples having good dispersibility can be obtained. The high strength polyethylene fibers of the present invention have excellent flexural fatigue resistance and excellent abrasion resistance, while having about the same or higher strength and Young's modulus than those of the conventional high strength polyethylene fibers; therefore, the high strength polyethylene fibers of the present invention are suitable for various ropes or cables for industrial or private use, particularly running cables used for a long period, such as mooring ropes and hawsers; blind cables; printer cables; and they are also useful as the materials for various sports gears and sportswears, such as fishing lines, tents, sports socks and uniforms, and various garments. The high strength polyethylene fibers of the present invention are also extremely useful for high performance textiles such as ballistic materials or items, or protective gloves because of their excellent cut resistance and excellent blade resistance arising from the above excellent characteristics. The high strength polyethylene fibers of the present invention are further useful in the chemical processes because of their having close surface and therefore having remarkably improved resistance to chemicals, light and weather, as compared with the conventional ultrahigh molecular weight polyethylene fibers, for example, as the chopped fibers to produce non-woven fabrics such as chemical filters or battery cell separators, which are required to have chemical resistance. The high strength polyethylene fibers of the present invention are still further useful as the reinforcing fibers in the composite materials for sports gears such as helmets and skis and for speaker cones, as the reinforcing materials for concrete or mortar, particularly spray-coated concrete or normal plane concrete in tunnels, or as the fibers for reinforcing sheets and strands to provide earthquake resistance. The ballistic materials or items of the present invention can be produced using the above novel high strength polyethylene fibers as the base yarns, which fibers may be mixed with other fibers known in the art. The ballistic materials or items of the present invention may be produced by, for example, weaving the base yarns into cloths, or paralleling the base yarns along one direction and then impregnating the paralleled yarns with resins, followed by layering to form sheets so that the paralleling direction for one sheet is perpendicular to that for the next sheet; and laminating such two or more cloths or sheets. Examples The present invention will be further illustrated by some examples; however, the present invention is not limited to these examples. First, the high strength polyethylene fibers of the present invention are exemplified by Examples 1 to 3 and Comparative Example 1 to 2. The polyethylene fibers prepared by these Examples and Comparative Examples were measured for their physical properties by the following measuring and testing methods, and evaluated for their performance. Intrinsic Viscosity Number of Fibers Using a capillary viscosity tube of the Ubbelohde type, dilute solutions of different concentrations were measured for viscosity in decalin at 135°C, and intrinsic viscosity number was determined by drawing a straight line on the plot of their specific viscosity against concentrations by the method of least squares and extrapolation of the straight line toward zero concentration. In the measurement of viscosity, a specimen was cut to about 5 mm in length, and an antioxidant (under the trade name "Yoshinox BHT" available from Yoshitomi Pharmaceutical Industries, Ltd.) was added in 1 wt% relative to the specimen, followed by stirring at 135°C for 4 hours for dissolution to give a solution for measurement. Strength and Young's Modulus of Fibers Using "Tensilon" available from Orientech Corp., a strain-stress curve was drawn under the conditions: length of specimen, 200 mm (gap distance between chucks); elongation rate, 100%/min.; atmospheric temperature, 20°C; and relative humidity, 65%; and strength (cN/dtex) was calculated from the stress at the breaking point on the curve obtained, and Young's modulus (cN/dtex) was calculated from the tangent line providing the maximum gradient on the curve in the vicinity of the origin. The number of measurements was set at 10, and the strength and Young's modulus were expressed by the respective averaged values. Differential Scanning Calorimetry (DSC) of Fibers Using "DSC7" available from Perkin-Elmer Corp. (the maximum sensitivity, 8 µW/cm), DSC was carried out as follows. A specimen was cut in 5 mm or shorter, and about 5 mg of the specimen was charged and sealed in an aluminum pan. The same, but vacant, aluminum pan was used as a reference. A temperature-increasing DSC curve was drawn by heating the specimen from room temperature up to 200°C at a heating rate of 10°C/min., under an atmosphere of an inert gas. The temperature-increasing DSC curve obtained was corrected for the base line, followed by reading the number of peaks, peak temperatures, and peak heights over a temperature region of 140°C to 148°C (on the low temperature side) and over a temperature region of 148°C or higher (on the high temperature side), and calculating the height ratio of the maximum endothermic peak on the low temperature side and the maximum endothermic peak on the high temperature side. If the endothermic peaks are difficult to read because of their shoulder-like shapes, the values of heat flow at 145.5°C and at 150°C were regarded as the endothermic peaks on the low temperature side and on the high temperature side, respectively, to calculate the ratio of peak heights. Abrasion Test of Fibers A specimen was prepared by multiplying or adjustment to have a linear density of about 1500 dtex and evaluated for abrasion resistance by an abrasion test according to method B for measuring abrasion resistance in the Testing Methods for Spun Yarns (JIS L 1095). Using a 0.9 mm tip of hard steel as a friction contact, each test was carried out under the conditions: load, 0.5 g/d; rate of friction, 115 times/min.; distance of reciprocating motion, 2.5 cm; and angle of friction, 110°. The abrasion resistance was determined as the number of frictions until a specimen was broken. The number of runs was set at 2, and the results were expressed by their average values. The values were rounded off to the third digit. Example 1 A slurry mixture of 10 wt% ultrahigh molecular weight polyethylene having an intrinsic viscosity number of 21.0 and a molecular weight distribution index (Mw/Mn) of 3.7 and 90 wt% decalin was fed to a screw-type kneader at 230°C, and their dissolution was achieved to give a spinning solution, followed by spinning at a rate of discharge through each nozzle of 1.4 g/min. using a spinneret (the diameter of each nozzle, 0.7 mm; the number of nozzles, 400) at 170°C. The discharged filaments were blown with a nitrogen gas at 100°C as uniformly as possible at an average flow rate of 1.2 m/sec. through a slit-shaped orifice for gas feed, which orifice was disposed just below the spinneret, so that the decalin in the fiber surface was positively evaporated. Immediately after that, the filaments were substantially cooled with an air flow at 30°C, and wound at a rate of 75 m/min. by Nelson-type rollers disposed downstream the spinneret. At that time, the solvent contained in the filaments had already reduced its weight by half from the original weight. Subsequently, the filaments obtained were drawn at a ratio of 4 in a heating oven at 100°C and further drawn at a ratio of 4 in a heating oven at 149°C, thereby obtaining a polyethylene fiber. The physical properties and performance evaluation of the fiber are shown in Table 1. The temperature-increasing DSC curve before base line correction, which was obtained by differential scanning calorimetry (DSC), is shown in Figure 1. Example 2 A polyethylene fiber was prepared in the same manner as described in Example 1, except that the discharged filaments were blown with a nitrogen gas at 120°C at an average flow rate of 1.4 m/sec. The physical properties and performance evaluation of the fiber are shown in Table 1. The temperature-increasing DSC curve before base line correction, which was obtained by differential scanning calorimetry (DSC), is shown in Figure 2. Example 3 A polyethylene fiber was prepared in the same manner as described in Example 1, except that a high molecular weight polyethylene having an intrinsic viscosity number of 12.1 and a molecular weight distribution index (Mw/Mn) of 5.4 was used; the concentration of a spinning solution was set at 30 wt%; and drawing was carried out at a ratio of 3 for the first stage and 2.2 for the second stage. The physical properties and performance evaluation of the fiber are shown in Table 1. The temperature-increasing DSC curve before base line correction, which was obtained by differential scanning calorimetry (DSC), is shown in Figure 3. Comparative Example 1 A polyethylene fiber was prepared in the same manner as described in Example 1, except that the discharged filaments were not blown just below the spinneret with a high temperature nitrogen gas, but were immediately cooled with a nitrogen gas at 30°C; and drawing was carried out at a ratio of 4.0 for the first stage and 3.5 for the second stage. The physical properties and performance evaluation of the fiber are shown in Table 1. The temperature-increasing DSC curve before base line correction, which was obtained by differential scanning calorimetry (DSC), is shown in Figure 4. Comparative Example 2 Spinning was carried out in the same manner as described in Example 1, except that paraffin oil was used as a solvent; and drawing was carried out at a ratio of 4, while the solvent was substantially extracted in a cooling bath containing n-decane at about 80°C, which bath was disposed just below the spinneret. No positive cooling with an inert gas was carried out. The semi-stretched filaments obtained were further drawn at a ratio of 4 in an oven at 145°C under an atmosphere of an inert gas, so that the n-decane contained was substantially evaporated, thereby obtaining a polyethylene fiber. The physical properties and performance evaluation of the fiber are shown in Table 1. The temperature-increasing DSC curve before base line correction, which was obtained by differential scanning calorimetry (DSC), is shown in Figure 5. As can be seen from Table 1, the polyethylene fibers of Examples 1 to 3 had extremely excellent abrasion resistance because of their 3.5 times larger numbers of frictions until the fibers were broken in the abrasion test, while exhibiting about the same or higher strength and Young's modulus, as compared with the polyethylene fibers of Comparative Examples 1 to 2. For the polyethylene fibers of Examples 1 to 3, the temperature-increasing DSC curves had one or two endothermic peaks on the high temperature side and one endothermic peak on the low temperature side. In contrast, for the polyethylene fiber of Comparative Example 1, the temperature-increasing DSC curve had no endothermic peak on the low temperature side, whereas no distinct peak but a shoulder was found as the endothermic peak on the high temperature side. For the polyethylene fiber of Comparative Example 2, the temperature-increasing DSC curve had one complete peak on the high temperature side, whereas no endothermic peak but a small shoulder around 133°C was observed on the low temperature side. For the polyethylene fibers of Comparative Examples 1 and 2, it is presumed that their maximum endothermic peaks on the high temperature side come from EC and not from HMC, because of their extremely deteriorated abrasion resistance. Now, the ballistic materials or items using the high strength polyethylene fibers of the present invention are exemplified in Example 4 and Comparative Example 3. The ballistic materials prepared in these Examples and Comparative Example were evaluated for their performance by the following ballistic test. Ballistic Test for Ballistic Materials A specimen of materials was cut into squares each measuring 20 cm in one side, and these squares were layered to have a weight of about 1 kg/m 2 and then peripherally fastened with over-locks to give a specimen for ballistic test. The ballistic test was carried out according to MIL-STD-662E. A 17-grain fragment simulating projectile as described in MIL-P-46593A was discharged at a speed of about 500 m/sec. from a barrel with a propellant to collide with the specimen. At that time, speeds V 1 and V 2 of the fragment simulating projectile before the collision with the specimen and after the penetration, respectively, were measured with a chronograph using a photo-screen. The impact resistance was evaluated by unit energy loss (SEA) calculated from the measured speeds V 1 and V 2 by the following equation. SEA = 1 / 2 × ( V 1 2 - V 2 2 ) × 0.0011 / sample weight The number of runs was set at 3, and the value of SEA was expressed by their average value. Example 4 The high strength polyethylene fiber obtained in Example 2 (intrinsic viscosity number, 18.4; linear density, 448 dtex; strength, 35.2 cN/dtex; Young's modulus, 1612 cN/dtex) was twisted to have a twist coefficient of 0.7, thereby obtaining a base yarn. A plain-woven fabric (weight, 180.6 g/m 2 ) with the numbers of warp yarns and weft yarns being both 48 yarns/25 mm was prepared with this base yarn. The ballistic material obtained was subjected to the ballistic test. The results are shown in Table 2. Comparative Example 3 A plain-woven fabric (weight, 188.1 g/m 2 ) was prepared in the same manner as described in Example 4, except that the high strength polyethylene fiber obtained in Comparative Example 2 (intrinsic viscosity number, 18.3; linear density, 471 dtex; strength, 35.7 cN/dtex; Young's modulus, 1623 cN/dtex) was used; and then subjected to the ballistic test. The results are shown in Table 2. Fabric weight (g/m 2 ) Number of layers (pieces) Weight of specimen (g/m 2 ) SEA (J/(kg/m 2 )) Example 4 180.6 6 1085 25.2 Example 3 188.1 6 1130 23.9 As can be seen from Table 2, the ballistic material of Example 4 exhibited higher unit energy loss; thereby it had excellent impact resistance, as compared with the ballistic material of Comparative Example 3 Industrial Applicability According to the present invention, high strength polyethylene fibers can be obtained, which have about the same or higher strength and Young's modulus than those of the conventional high strength polyethylene fibers, and at the same time, have excellent durability, particularly flexural fatigue resistance and excellent abrasion resistance. Such high strength polyethylene fibers can be widely applied as the materials for high performance ballistic materials or items.

Claims: A ballistic material comprising high strength polyethylene fibers characterized in that : the fiber comprises a high molecular weight polyethylene consisting essentially of a repeating unit of ethylene; it has an intrinsic viscosity number of 5 or larger and an average strength of 22 cN/dtex or higher; and the measurement of the fiber by differential scanning calorimetry (DSC) exhibits a temperature-increasing DCS curve having at least one endothermic peak over a temperature region of 140°C to 148°C (on the low temperature side) and at least one endothermic peak over a temperature region of 148°C or higher (on the high temperature side). The ballistic material according to claim 1, wherein the height ratio of the maximum endothermic peak on the low temperature side and the maximum endothermic peak on the high temperature side is 1.4 : 1.0 to 3.0 : 1.0. The ballistic material according to claim 2, wherein the height ratio of the maximum endothermic peak on the low temperature side and the maximum endothermic peak on the high temperature side is 1.5 : 1.0 to 2.9 : 1.0. A ballistic material comprising high strength polyethylene fibers characterized in that : the fiber comprises a high molecular weight polyethylene consisting essentially of a repeating unit of ethylene; it has an intrinsic viscosity number of 5 or larger and an average strength of 22 cN/dtex or higher; and the number of frictions until the fiber is broken in an abrasion test according to method B for measuring abrasion resistance in Testing Methods for Spun Yarn (JIS L 1095) is 100,000 or larger.

Inventors: NOMURA YUKIHIRO, NOMURA, YUKIHIRO
Applicants: TOYO BOSEKI, TOYO BOSEKI KABUSHIKI KAISHA
Application year: 2000
Main classification: D01F6
IPC codes: D04G1, A41D13, A41D31, D04B21, C04B16, D01F6, D07B1, D04C1, A41D19