Reactive Ni–Al-Based Materials: Strength and Combustion Behavior

The effect of PTFE, continuous boron, and tungsten fibers on the combustion behavior and strength of reactive Ni–Al compacts was examined in this study. The introduction of continuous fibers into Ni–Al compacts according to the developed scheme was found to increase the flexural strength from 12 to 120 MPa. Heat treatment (HT), leading to chemical interaction of the starting components, increases the strength of compacts at temperatures not exceeding 550 °C. The combination of reinforcement and HT significantly increases the strength without reducing reactivity. Experimental results showed that strength and combustion rate increase with the reduction in PTFE to 1 wt % in Ni–Al compacts. A favorable effect of the addition of PTFE from 5 to 10 wt % on the reduction of the threshold for the shock-wave initiation of reactions in Ni–Al was established. The obtained results can be used to produce reactive materials with high mechanical and energy characteristics.


Introduction
Energetic materials are substances or mixtures in which, under the action of external forces, self-sustaining chemical reactions occur with the release of a large amount of energy. A promising group of energetic materials are reactive structural materials (RSMs), consisting of two or more solids, usually nonexplosive metallic or nonmetallic powders, in which an exothermic reaction can occur after high-velocity impact and penetration into a target. As a rule, thermite, intermetallic, metal-fluoropolymer systems and metastable intermixed composites are used as RSMs [1,2].
These materials can be used in the military field as kinetic penetrators, cumulative highly reactive fragments, shaped charge liners [3], reactive projectiles, and reactive (active) armor and munition bodies [1,2,4]. RSMs must have mechanical properties comparable to traditional materials, such as steel, aluminum, copper, etc., which have a tensile strength of no less than 100 MPa. The most promising in terms of high strength are intermetallic systems. The compositions of Ni-Al, Al-W, Al-Zr, etc., in addition to high energy concentration, possess structural strength [3,5]. Since RSM components, as a rule, are powders, they must be consolidated. There are various technologies to consolidate RSMs into a monolithic structure: radial forging [1,6], cold and hot isostatic pressing [7,8], high-pressure torsion [9], magnetron sputtering [10] and cold spraying [11,12], cold rolling [13,14], accumulative roll-bonding [15], and explosive compacting [5,16]. The disadvantages of sputtering are its low rate and high cost. High-pressure processing requires large-sized equipment and includes multi-stage plastic deformation of two materials with different plasticity, which can eventually lead to material cracking and partial chemical interaction between starting components.

Materials and Methods
Powders of PTFE (F-4NTD-2 grade, particle size < 5 µm), aluminum (ASD-1 grade, particle size < 50 µm) and nickel (PNK-UT3 grade, particle size < 50 µm) were used as starting components. Calculations of the optimal RSM composition were performed using THERMO software [40]. Thermodynamic equilibrium conditions in a multi-component heterogeneous system were determined using the minimization procedure of the thermodynamic potential (free energy) of the system, considering the restrictions associated with the laws of conservation of mass of chemical elements. The powders were mixed in a tumbling drum mixer for 3 h at 30 rpm with a ball-to-powder weight ratio of 5:1. The specimens were compacted by single-action pressing using a hydraulic hand press (PRG-10, Lab Tools, St. Petersburg, Russia).
Then, the inert and active fillers, i.e., tungsten and boron fibers with a diameter of 0.3 mm and 0.14 mm, were introduced into the powder compacts. The reinforcement scheme and the picture of Ni-Al and Ni-Al-PTFE powder compacts are shown in Figure 1. To prepare one specimen, the mixture was divided into 5 equal parts and placed layer by layer into the mold. The fibers were then placed on each layer except for the last one.
The number of fiber layers was constant and was equal to four, as shown in Figure 1a, and the number of fibers in one layer of the specimen was chosen experimentally. The number of fibers in a monolayer was limited by the specimen's size. The specimens had the shape of a parallelepiped with dimensions of 5 × 5 × 20 mm. The PTFE content was chosen experimentally and varied according to the formula (100×) (Ni-Al) + xPTFE. The types and compositions of specimens are shown in Table 1. Three types of specimens were made of the Ni-Al powder mixture: a, unreinforced; b, reinforced with boron; and c, reinforced with tungsten fibers with relative densities of 0.7 and 0.8. The density of the specimens was determined from their geometric dimensions (micrometer by Dasqua, Cornegliano Laudense, Italy) and weight (CAS XE-300 analytical balance, CAS, East Rutherford, NJ, USA). The relative density was calculated as the ratio of the actual to the theoretically possible [41]. Two types of specimens were fabricated of the Ni-Al-PTFE powder mixture: d, unreinforced; and e, reinforced with boron fibers with a relative density ranging from 0.84 to 0.99. The specimens constructed of the Ni-Al mixture with a relative density of 0.7 were subjected to HT in the modes described in Table 2.
Metals 2021, 11, x FOR PEER REVIEW 3 of 16 theoretically possible [41]. Two types of specimens were fabricated of the Ni-Al-PTFE powder mixture: d, unreinforced; and e, reinforced with boron fibers with a relative density ranging from 0.84 to 0.99. The specimens constructed of the Ni-Al mixture with a relative density of 0.7 were subjected to HT in the modes described in Table 2.
(a) (b)    Time, h  Temperature of Heating, °C  1  300  400  500  550  2  300  400  500  550  3  300  400  500  550 The flexural strength of the specimens was determined from a three-point bending test (according to the GOST 25282-93 standard) using the universal testing machine (Instron 1195, V = 2 mm/min, Figure 2). The flexural strength was calculated according to the following formula: where P is applied load (H), l is distance between supports (mm), h is specimen height (mm), and b is specimen width (mm). The specimens with a diameter of 3 mm and a height of 1-2 mm were pressed to study the ignition process. The experiments were performed in a reactor in a protective argon (Ar) atmosphere at atmospheric pressure ( Figure 3). The reactor was sealed with a lid with a quartz viewing window. A graphite plate 10 mm in width, 1 mm in thickness, and 20-25 mm in length served as a heater through which an electric current was passed    1  300  400  500  550  2  300  400  500  550  3  300  400  500  550 The flexural strength of the specimens was determined from a three-point bending test (according to the GOST 25282-93 standard) using the universal testing machine (Instron 1195, V = 2 mm/min, Figure 2). The flexural strength was calculated according to the following formula: where P is applied load (H), l is distance between supports (mm), h is specimen height (mm), and b is specimen width (mm). The specimens with a diameter of 3 mm and a height of 1-2 mm were pressed to study the ignition process. The experiments were performed in a reactor in a protective argon (Ar) atmosphere at atmospheric pressure ( Figure 3). The reactor was sealed with a lid with a quartz viewing window. A graphite plate 10 mm in width, 1 mm in thickness, and 20-25 mm in length served as a heater through which an electric current was passed from an autotransformer. A boron nitride crucible with a flat thermocouple welded from WR5/WR20 thermocouple wires with an original diameter of 100 µm was placed on the heater, followed by rolling to a thickness of 50 µm. The specimen under study was placed on the thermocouple and heated by convective and radiation heat flow from the crucible at a rate of 40-60 • C/s. The specimen temperature was recorded on a computer using an analog-to-digital converter (ADC) [42]. This procedure determines the intensity of exothermic reaction and phase transitions in the specimen, similar to differential scanning calorimetry (DSC) and differential thermal analysis (DTA) used in the works [37,[43][44][45]. The phase composition of the products was characterized by X-ray diffraction (XRD, DRON-3M, Burevestnik, St. Petersburg, Russia). The samples were scanned from 20 • to 80 • (2Θ) with a scanning step of 0.02 • .
from an autotransformer. A boron nitride crucible with a flat thermocouple welded from WR5/WR20 thermocouple wires with an original diameter of 100 µm was placed on the heater, followed by rolling to a thickness of 50 µm. The specimen under study was placed on the thermocouple and heated by convective and radiation heat flow from the crucible at a rate of 40-60 °C/s. The specimen temperature was recorded on a computer using an analog-to-digital converter (ADC) [42]. This procedure determines the intensity of exothermic reaction and phase transitions in the specimen, similar to differential scanning calorimetry (DSC) and differential thermal analysis (DTA) used in the works [37,[43][44][45]. The phase composition of the products was characterized by X-ray diffraction (XRD, DRON-3M, Burevestnik, St. Petersburg, Russia). The samples were scanned from 20° to 80° (2Θ) with a scanning step of 0.02°.  The temperature and linear rate of combustion were determined in a 20 L reactor with the possibility of creating both an inert atmosphere (Ar) and vacuum up to 2 × 10 4 Pa. A schematic of the reactor and experimental bench is shown in Figure 4. In this experiment, 5 × 5 × 20 mm specimens were used, and 100 µm diameter WR5/WR20 thermocouple wires were applied to measure the exothermic reaction temperature. Two blind holes, 0.3-0.5 mm in diameter and 2 mm in depth, were predrilled in the specimens at 4-5 mm from the top and 1-2 mm from the end. The specimen was placed on a refractory table close to the graphite heater, and then thermocouples were introduced into it. The necessary atmosphere was created in the reactor to activate the specimen. The thermocouple readings were converted using ADC and sent to a computer for processing.
Experiments on shockwave initiation of reactive materials were conducted by throwing a steel plate (3) (3 mm thick) accelerated by the explosive (2) to the surface of a matrix (4) that contained cylindrical specimens (5) with a diameter of 10 mm and a height of 10 mm ( Figure 5). The explosive was activated by an electric detonator placed along from an autotransformer. A boron nitride crucible with a flat thermocouple welded from WR5/WR20 thermocouple wires with an original diameter of 100 µm was placed on the heater, followed by rolling to a thickness of 50 µm. The specimen under study was placed on the thermocouple and heated by convective and radiation heat flow from the crucible at a rate of 40-60 °C/s. The specimen temperature was recorded on a computer using an analog-to-digital converter (ADC) [42]. This procedure determines the intensity of exothermic reaction and phase transitions in the specimen, similar to differential scanning calorimetry (DSC) and differential thermal analysis (DTA) used in the works [37,[43][44][45]. The phase composition of the products was characterized by X-ray diffraction (XRD, DRON-3M, Burevestnik, St. Petersburg, Russia). The samples were scanned from 20° to 80° (2Θ) with a scanning step of 0.02°.  The temperature and linear rate of combustion were determined in a 20 L reactor with the possibility of creating both an inert atmosphere (Ar) and vacuum up to 2 × 10 4 Pa. A schematic of the reactor and experimental bench is shown in Figure 4. In this experiment, 5 × 5 × 20 mm specimens were used, and 100 µm diameter WR5/WR20 thermocouple wires were applied to measure the exothermic reaction temperature. Two blind holes, 0.3-0.5 mm in diameter and 2 mm in depth, were predrilled in the specimens at 4-5 mm from the top and 1-2 mm from the end. The specimen was placed on a refractory table close to the graphite heater, and then thermocouples were introduced into it. The necessary atmosphere was created in the reactor to activate the specimen. The thermocouple readings were converted using ADC and sent to a computer for processing.
Experiments on shockwave initiation of reactive materials were conducted by throwing a steel plate (3) (3 mm thick) accelerated by the explosive (2) to the surface of a matrix (4) that contained cylindrical specimens (5) with a diameter of 10 mm and a height of 10 mm ( Figure 5). The explosive was activated by an electric detonator placed along The temperature and linear rate of combustion were determined in a 20 L reactor with the possibility of creating both an inert atmosphere (Ar) and vacuum up to 2 × 10 4 Pa. A schematic of the reactor and experimental bench is shown in Figure 4. In this experiment, 5 × 5 × 20 mm specimens were used, and 100 µm diameter WR5/WR20 thermocouple wires were applied to measure the exothermic reaction temperature. Two blind holes, 0.3-0.5 mm in diameter and 2 mm in depth, were predrilled in the specimens at 4-5 mm from the top and 1-2 mm from the end. The specimen was placed on a refractory table close to the graphite heater, and then thermocouples were introduced into it. The necessary atmosphere was created in the reactor to activate the specimen. The thermocouple readings were converted using ADC and sent to a computer for processing.
Experiments on shockwave initiation of reactive materials were conducted by throwing a steel plate (3) (3 mm thick) accelerated by the explosive (2) to the surface of a matrix (4) that contained cylindrical specimens (5) with a diameter of 10 mm and a height of 10 mm ( Figure 5). The explosive was activated by an electric detonator placed along the axis of the setup. Blind holes were drilled in a steel matrix with the dimensions of 20 × 100 × 100 mm equidistant from the center to ensure the same loading conditions in all cells with specimens. During shockwave loading, a steel plate was welded to the matrix, ensuring that the specimens were preserved and could be further examined. Flyer plate (steel) velocities were 1.0 and 1.5 km/s. the axis of the setup. Blind holes were drilled in a steel matrix with the dimensions of 20 × 100 × 100 mm equidistant from the center to ensure the same loading conditions in all cells with specimens. During shockwave loading, a steel plate was welded to the matrix, ensuring that the specimens were preserved and could be further examined. Flyer plate (steel) velocities were 1.0 and 1.5 km/s.

Results
The above-described procedure was used to prepare the specimens reinforced with continuous boron and tungsten fibers with powder matrices Ni-Al and Ni-Al-PTFE. Thermodynamic calculations were performed to select the stoichiometric composition of Ni-Al with the highest adiabatic combustion temperature (1638 °C). We found that the strength characteristics of the prepared specimens, namely the flexural strength of powder compacts with different molar ratios of nickel and aluminum (Ni-3Al, Ni-Al, and 3Ni-Al), are identical and lie in the range of 11 to 13 MPa at a relative density of 0.7. So, the choice of a Ni-Al stoichiometric composition is not only due to the high adiabatic combustion temperature, but also due to the strength.
For reinforced specimens, the optimal arrangement of fibers, which was determined experimentally, is of great importance. Laying one or two fibers did not provide a significant increase in strength. An excessive number of fibers reduces the strength charac- the axis of the setup. Blind holes were drilled in a steel matrix with the dimensions of 20 × 100 × 100 mm equidistant from the center to ensure the same loading conditions in all cells with specimens. During shockwave loading, a steel plate was welded to the matrix, ensuring that the specimens were preserved and could be further examined. Flyer plate (steel) velocities were 1.0 and 1.5 km/s.

Results
The above-described procedure was used to prepare the specimens reinforced with continuous boron and tungsten fibers with powder matrices Ni-Al and Ni-Al-PTFE. Thermodynamic calculations were performed to select the stoichiometric composition of Ni-Al with the highest adiabatic combustion temperature (1638 °C). We found that the strength characteristics of the prepared specimens, namely the flexural strength of powder compacts with different molar ratios of nickel and aluminum (Ni-3Al, Ni-Al, and 3Ni-Al), are identical and lie in the range of 11 to 13 MPa at a relative density of 0.7. So, the choice of a Ni-Al stoichiometric composition is not only due to the high adiabatic combustion temperature, but also due to the strength.
For reinforced specimens, the optimal arrangement of fibers, which was determined experimentally, is of great importance. Laying one or two fibers did not provide a significant increase in strength. An excessive number of fibers reduces the strength charac-

Results
The above-described procedure was used to prepare the specimens reinforced with continuous boron and tungsten fibers with powder matrices Ni-Al and Ni-Al-PTFE. Thermodynamic calculations were performed to select the stoichiometric composition of Ni-Al with the highest adiabatic combustion temperature (1638 • C). We found that the strength characteristics of the prepared specimens, namely the flexural strength of powder compacts with different molar ratios of nickel and aluminum (Ni-3Al, Ni-Al, and 3Ni-Al), are identical and lie in the range of 11 to 13 MPa at a relative density of 0.7. So, the choice of a Ni-Al stoichiometric composition is not only due to the high adiabatic combustion temperature, but also due to the strength.
For reinforced specimens, the optimal arrangement of fibers, which was determined experimentally, is of great importance. Laying one or two fibers did not provide a significant increase in strength. An excessive number of fibers reduces the strength characteristics of the material. The optimal number of fibers per layer for each fiber type is shown in Figure 6. Figure 7 shows the strength characteristics for different specimen types as a function of density. We found that increasing the density of compacts by 10% increased the strength of unreinforced specimens by 190%, with boron fibers by 170%, and with tungsten fibers by 65%. The boron fibers increased the strength by 60% and the tungsten fibers by 200% compared with unreinforced specimens. The reason for the increased strength of powder compacts is related to the redistribution of the load from the matrix to the Metals 2021, 11, 949 6 of 14 fiber due to mechanical interlocking and friction between the powder and the fibers. It is necessary to note that there is a problem of insufficient adhesion of fiber with the matrix. This phenomenon mainly occurs with boron fibers. So, when bending, they are pulled out from the matrix without being destroyed, and as a result, are not possible to use to their full potential.
teristics of the material. The optimal number of fibers per layer for each fiber type is shown in Figure 6. Figure 7 shows the strength characteristics for different specimen types as a function of density. We found that increasing the density of compacts by 10% increased the strength of unreinforced specimens by 190%, with boron fibers by 170%, and with tungsten fibers by 65%. The boron fibers increased the strength by 60% and the tungsten fibers by 200% compared with unreinforced specimens. The reason for the increased strength of powder compacts is related to the redistribution of the load from the matrix to the fiber due to mechanical interlocking and friction between the powder and the fibers. It is necessary to note that there is a problem of insufficient adhesion of fiber with the matrix. This phenomenon mainly occurs with boron fibers. So, when bending, they are pulled out from the matrix without being destroyed, and as a result, are not possible to use to their full potential.  The dependencies of flexural strength of the specimens on the type of reinforcement and HT modes are shown in Figure 8. HT of specimens in air provided a significant increase in flexural strength from 12 to 100 MPa for unreinforced specimens, but for specimens reinforced with boron fibers, it had no positive effect due to the weakening of the fibers [46].
HT of type a specimens increased their strength by 40% at 300 °C for 2 h, by 350% at 400 °C for 2 h, by 650% at 500 °C for 1 h, and by 730% at 550 °C for 2-3 h. Before HT, the in flexural strength from 12 to 100 MPa for unreinforced specimens, but for specimens reinforced with boron fibers, it had no positive effect due to the weakening of the fibers [46].
HT of type a specimens increased their strength by 40% at 300 • C for 2 h, by 350% at 400 • C for 2 h, by 650% at 500 • C for 1 h, and by 730% at 550 • C for 2-3 h. Before HT, the type b specimens had an average strength of 23 MPa. The strength of the specimens increased by 90% at 400 • C for 2 h and by 250% at 500 • C for 2 h. The tungsten-fiberreinforced specimens had an average strength of 60 MPa before HT, and after HT, the strength increased by 80% to 110 MPa at 400 • C for 3 h. HT of type a and c specimens provided hardening due to sintering of material, which is caused by the reduction in voids in the specimen, consequently resulting in denser and stronger material. Specimens subjected to HT for 1 h at 400 and 500 °C contained NiO, and at 550 °C, in addition to the oxidation of nickel, a partial synthesis of the starting components with the formation of intermetallic compounds (Ni2Al3, NiAl3) occurred, as seen in the X-ray diffraction patterns (Figure 9). A similar effect is observed for magnetron sputtering [10] and shockwave loading [5], which reduces the number of reactive components. Figure 10 shows the dependence of strength of the powder Ni-Al-PTFE compacts on the proportion of PTFE and the type of reinforcement (relative density is provided for each specimen). The content of 1 wt % PTFE in the Ni-Al compact reinforced with boron fibers led to an increase in strength by 30% and to a decrease in strength by 30-35% for 3-5 wt % PTFE. Increasing the proportion of PTFE in the Ni-Al specimens increased the relative density, but it had a negative effect on their strength characteristics due to the low friction coefficient of PTFE. Specimens subjected to HT for 1 h at 400 and 500 • C contained NiO, and at 550 • C, in addition to the oxidation of nickel, a partial synthesis of the starting components with the formation of intermetallic compounds (Ni 2 Al 3 , NiAl 3 ) occurred, as seen in the X-ray diffraction patterns (Figure 9). A similar effect is observed for magnetron sputtering [10] and shockwave loading [5], which reduces the number of reactive components. Figure 10 shows the dependence of strength of the powder Ni-Al-PTFE compacts on the proportion of PTFE and the type of reinforcement (relative density is provided for each specimen). The content of 1 wt % PTFE in the Ni-Al compact reinforced with boron fibers led to an increase in strength by 30% and to a decrease in strength by 30-35% for 3-5 wt % PTFE. Increasing the proportion of PTFE in the Ni-Al specimens increased the relative density, but it had a negative effect on their strength characteristics due to the low friction coefficient of PTFE.        Figure 11 shows the fracture of Ni-Al and Ni-Al-PTFE specimens with different types of reinforcement. The specimens of type a have a brittle and fast fracture. The specimens of type b fractured gradually along with pulling, bending, and breaking.
The investigation of the ignition of Ni-Al and Ni-Al-PTFE specimens before and after HT is shown in Figure 12 and Table 3, respectively. We found that the Ni-Al mixture ignited at about 660 • C, which corresponds to the melting temperature of Al and agrees with the results of DTA and DSC in the works [11,12,43,45]. After HT of the Ni-Al specimens, the ignition temperature increased from 660 to 980 • C, which is associated with the formation of oxide films on the surface of aluminum and nickel particles, preventing the aluminum from melting and spreading over nickel. In the Ni-Al-PTFE specimens, the ignition temperature was about 620-640 • C. According to the data of [43], at a heating rate of 10 • C/min, the reaction proceeded at 585 • C. In the present experiments, the recorded temperature was higher due to the high heating rate, as explained by the authors in [42]. The ignition temperature can be reduced using nanosized powders [47] or high-energy ball milling (HEBM) [10,48] and cryomixing [49]. The use of nanopowders is associated with difficulties such as agglomeration and autoignition in air. HEBM of powders leads to the synthesis of some starting components and reduces the formability of powder compacts as well. The investigation of the ignition of Ni-Al and Ni-Al-PTFE specimens before and after HT is shown in Figure 12 and Table 3, respectively. We found that the Ni-Al mixture ignited at about 660 °C, which corresponds to the melting temperature of Al and agrees with the results of DTA and DSC in the works [11,12,43,45]. After HT of the Ni-Al specimens, the ignition temperature increased from 660 to 980 °C, which is associated with the formation of oxide films on the surface of aluminum and nickel particles, preventing the aluminum from melting and spreading over nickel. In the Ni-Al-PTFE specimens, the ignition temperature was about 620-640 °C. According to the data of [43], at a heating rate of 10 °C/min, the reaction proceeded at 585 °C. In the present experiments, the recorded temperature was higher due to the high heating rate, as explained by the authors in [42]. The ignition temperature can be reduced using nanosized powders [47] or high-energy ball milling (HEBM) [10,48] and cryomixing [49]. The use of nanopowders is associated with difficulties such as agglomeration and autoignition in air. HEBM of powders leads to the synthesis of some starting components and reduces the formability of powder compacts as well.    The investigation of the ignition of Ni-Al and Ni-Al-PTFE specimens before and after HT is shown in Figure 12 and Table 3, respectively. We found that the Ni-Al mixture ignited at about 660 °C, which corresponds to the melting temperature of Al and agrees with the results of DTA and DSC in the works [11,12,43,45]. After HT of the Ni-Al specimens, the ignition temperature increased from 660 to 980 °C, which is associated with the formation of oxide films on the surface of aluminum and nickel particles, preventing the aluminum from melting and spreading over nickel. In the Ni-Al-PTFE specimens, the ignition temperature was about 620-640 °C. According to the data of [43], at a heating rate of 10 °C/min, the reaction proceeded at 585 °C. In the present experiments, the recorded temperature was higher due to the high heating rate, as explained by the authors in [42]. The ignition temperature can be reduced using nanosized powders [47] or high-energy ball milling (HEBM) [10,48] and cryomixing [49]. The use of nanopowders is associated with difficulties such as agglomeration and autoignition in air. HEBM of powders leads to the synthesis of some starting components and reduces the formability of powder compacts as well.    Combustion rate measurements showed that increasing the relative density of type a compacts from 0.7 to 0.8 led to an increase in the combustion rate by 25% (Figure 13). The addition of 1 wt % PTFE to the Ni-Al powder mixture led to an increase in the combustion rate from 35 to 120 mm/s, which is comparable to that of thin aluminum-fluoropolymer films studied in [50]. When the PTFE proportion increased from 15 to 25 wt %, the combustion rate decreased to 1.5 mm/s. This effect is associated with gas evolution in the combustion wavefront, which leads to the loosening of the specimen and interruption of heat exchange. Figure 14 shows the X-ray diffraction patterns of the burned Ni-Al-PTFE specimens. The only synthesis product is NiAl. During combustion, a large amount of gaseous products is formed, which are deposited on the reactor walls, but their presence in the specimens was not detected.
Combustion rate measurements showed that increasing the relative density of type a compacts from 0.7 to 0.8 led to an increase in the combustion rate by 25% (Figure 13). The addition of 1 wt % PTFE to the Ni-Al powder mixture led to an increase in the combustion rate from 35 to 120 mm/s, which is comparable to that of thin aluminumfluoropolymer films studied in [50]. When the PTFE proportion increased from 15 to 25 wt %, the combustion rate decreased to 1.5 mm/s. This effect is associated with gas evolution in the combustion wavefront, which leads to the loosening of the specimen and interruption of heat exchange. Figure 14 shows the X-ray diffraction patterns of the burned Ni-Al-PTFE specimens. The only synthesis product is NiAl. During combustion, a large amount of gaseous products is formed, which are deposited on the reactor walls, but their presence in the specimens was not detected.   Combustion rate measurements showed that increasing the relative density of type a compacts from 0.7 to 0.8 led to an increase in the combustion rate by 25% (Figure 13). The addition of 1 wt % PTFE to the Ni-Al powder mixture led to an increase in the combustion rate from 35 to 120 mm/s, which is comparable to that of thin aluminumfluoropolymer films studied in [50]. When the PTFE proportion increased from 15 to 25 wt %, the combustion rate decreased to 1.5 mm/s. This effect is associated with gas evolution in the combustion wavefront, which leads to the loosening of the specimen and interruption of heat exchange. Figure 14 shows the X-ray diffraction patterns of the burned Ni-Al-PTFE specimens. The only synthesis product is NiAl. During combustion, a large amount of gaseous products is formed, which are deposited on the reactor walls, but their presence in the specimens was not detected.    Figure 15 shows the video frames of combustion in the Ni-Al and Ni-Al-PTFE powder systems with different types of reinforcement. During the combustion of the Ni-Al specimens, there was no significant gas evolution or change in size, in contrast with specimens with the addition of fluoroplastic which significantly changed the initial size and mass. Combustion of the Ni-Al specimens with the introduction of boron fibers noticeably changed, demonstrating a rapid separation of hot particles from the surface of the sample.
Combustion of Ni-Al with the addition of 1 and 3 wt % PTFE occurred with active heat release characterized by high temperature and high gasification of combustion products. Figure 15 shows the video frames of combustion in the Ni-Al and Ni-Al-PTFE powder systems with different types of reinforcement. During the combustion of the Ni-Al specimens, there was no significant gas evolution or change in size, in contrast with specimens with the addition of fluoroplastic which significantly changed the initial size and mass. Combustion of the Ni-Al specimens with the introduction of boron fibers noticeably changed, demonstrating a rapid separation of hot particles from the surface of the sample. Combustion of Ni-Al with the addition of 1 and 3 wt % PTFE occurred with active heat release characterized by high temperature and high gasification of combustion products. Synthesis in the Ni-Al and Ni-Al-PTFE systems subjected to shockwave loading was determined by visual inspection and XRD. Visual inspection revealed that shockwave loading of Ni-Al specimens, as well as with the addition of 1 and 3 wt % PTFE at throwing speeds of 1.0 and 1.5 km/s, did not result in combustion (Figure 16). At the throwing speed of 1.5 km/s, 5 wt % PTFE addition was sufficient to initiate the reaction (Figure 17), and at 1.0 km/s-10 wt % PTFE ( Figure 16). Thus, the addition of PTFE lowers the threshold of initiation of shock waves in the Ni-Al system, positively affecting its reactivity.  Synthesis in the Ni-Al and Ni-Al-PTFE systems subjected to shockwave loading was determined by visual inspection and XRD. Visual inspection revealed that shockwave loading of Ni-Al specimens, as well as with the addition of 1 and 3 wt % PTFE at throwing speeds of 1.0 and 1.5 km/s, did not result in combustion (Figure 16). At the throwing speed of 1.5 km/s, 5 wt % PTFE addition was sufficient to initiate the reaction (Figure 17), and at 1.0 km/s-10 wt % PTFE ( Figure 16). Thus, the addition of PTFE lowers the threshold of initiation of shock waves in the Ni-Al system, positively affecting its reactivity. Figure 15 shows the video frames of combustion in the Ni-Al and Ni-Al-PTFE powder systems with different types of reinforcement. During the combustion of the Ni-Al specimens, there was no significant gas evolution or change in size, in contrast with specimens with the addition of fluoroplastic which significantly changed the initial size and mass. Combustion of the Ni-Al specimens with the introduction of boron fibers noticeably changed, demonstrating a rapid separation of hot particles from the surface of the sample. Combustion of Ni-Al with the addition of 1 and 3 wt % PTFE occurred with active heat release characterized by high temperature and high gasification of combustion products. Synthesis in the Ni-Al and Ni-Al-PTFE systems subjected to shockwave loading was determined by visual inspection and XRD. Visual inspection revealed that shockwave loading of Ni-Al specimens, as well as with the addition of 1 and 3 wt % PTFE at throwing speeds of 1.0 and 1.5 km/s, did not result in combustion (Figure 16). At the throwing speed of 1.5 km/s, 5 wt % PTFE addition was sufficient to initiate the reaction (Figure 17), and at 1.0 km/s-10 wt % PTFE ( Figure 16). Thus, the addition of PTFE lowers the threshold of initiation of shock waves in the Ni-Al system, positively affecting its reactivity.

Conclusions
For the first time, the possibility of reinforcing reactive powder compacts with continuous fibers for increasing their strength characteristics was experimentally shown. The optimal schemes of reinforcement of RSM with boron and tungsten fibers, which increase the strength by 60% and 200%, were experimentally determined.
HT of Ni-Al at 400 °C and 550 °C for 3 h increased the ignition temperature to 740 °C and 980 °C, respectively. We found that HT of Ni-Al at temperatures of 400 and 500 °C for 1-3 h increases the strength by 650%, but it does not lead to chemical interaction between starting components. HT at 550 °C for 2-3 h increases the strength by 730%, but it leads to chemical interaction between starting components with the formation of NiAl3 and Ni2Al3. The obtained results can be used to control the mechanical characteristics of reactive powder materials without reducing their reactivity. The strength of the specimens was 100-120 MPa, which is comparable to that of aluminum.
Adding PTFE up to 1 wt % to the Ni-Al specimens reinforced with boron fibers increases the strength by 27% by reducing porosity, but at more than 3 wt % PTFE decreases the strength by 30%. The addition of fluoroplastic to the Ni-Al specimens makes it possible to obtain materials with relative density up to 0.99 at relatively low pressures, which cannot be achieved without this addition.
We found that the addition of 5% and 10% PTFE to the Ni-Al system is sufficient to initiate an exothermic reaction at flyer plate velocities of 1.5 and 1.0 km/s.

Conclusions
For the first time, the possibility of reinforcing reactive powder compacts with continuous fibers for increasing their strength characteristics was experimentally shown. The optimal schemes of reinforcement of RSM with boron and tungsten fibers, which increase the strength by 60% and 200%, were experimentally determined.
HT of Ni-Al at 400 • C and 550 • C for 3 h increased the ignition temperature to 740 • C and 980 • C, respectively. We found that HT of Ni-Al at temperatures of 400 and 500 • C for 1-3 h increases the strength by 650%, but it does not lead to chemical interaction between starting components. HT at 550 • C for 2-3 h increases the strength by 730%, but it leads to chemical interaction between starting components with the formation of NiAl 3 and Ni 2 Al 3 . The obtained results can be used to control the mechanical characteristics of reactive powder materials without reducing their reactivity. The strength of the specimens was 100-120 MPa, which is comparable to that of aluminum.
Adding PTFE up to 1 wt % to the Ni-Al specimens reinforced with boron fibers increases the strength by 27% by reducing porosity, but at more than 3 wt % PTFE decreases the strength by 30%. The addition of fluoroplastic to the Ni-Al specimens makes it possible to obtain materials with relative density up to 0.99 at relatively low pressures, which cannot be achieved without this addition.
We found that the addition of 5% and 10% PTFE to the Ni-Al system is sufficient to initiate an exothermic reaction at flyer plate velocities of 1.5 and 1.0 km/s.