1. Introduction
To attack a target underground, a tandem warhead with a shaped charge as the front charge is typically used. When a shaped charge is used as the forward charge in a tandem warhead to penetrate rock and soil, a large hole diameter of the penetration is vital. The hole diameter of penetration of the front charge has a significant effect on the penetration ability of the follow-through charge. Furthermore, the hole diameter of a normally shaped charge should be no more than 0.6 times the charge diameter (CD). When the diameter of the penetration hole is more than 0.7 CD, the depth of penetration (DOP) of the follow-through charge is increased significantly.
Amorphous alloys are a class of crystalline metals produced by avoiding crystallization during the solidification process of metals. They have high-strength properties, high toughness, and good process formability. The strengths of Zr-based amorphous materials show a trend of first decreasing and then increasing with increased strain rate; when the strain rate is about 3000 s−1, the shear deformation mechanism of Zr-based amorphous materials changes, and the deformation mode is similar to that of Zr-based crystalline materials. These materials exhibit the strain-hardening mechanism of crystalline materials. Moreover, with increased strain rate, the nanocrystal content gradually increases, strain hardening intensifies, and the compressive strength increases. Furthermore, a Zr-based amorphous alloy material can be used as the liner material. Consequently, the liner can form a high-speed particle flow driven by the explosive. When penetrating reinforced concrete, the high-speed particle jet can form a large penetration hole (0.7 times the diameter of the charge), enabling continuous penetration of the warhead with the use of a rear warhead.
Amorphous alloy materials have good mechanical and physical properties, such as high strength, hardness, and bending strength, as well as good wear resistance, fracture toughness, and corrosion resistance. This is because their microstructures show short-range order, long-range disorder, and no defects such as dislocations and vacancies; they are metastable structures. These materials have been extensively studied in the past few decades. However, almost all amorphous alloy materials are considered brittle materials at temperatures in the range of 23 °C–25 °C, owing to the local deformation caused by the infinite expansion of their single shear bands, which severely limits their application as structural materials. Therefore, before conducting engineering application research on bulk Zr-based amorphous alloy materials, mechanical property analysis should be carried out.
Bruck [
1] and other scholars found that the mechanical properties of Zr
41.2Ti
13.8Ni
10Cu
20Be
22.5 bulk amorphous alloy are not sensitive to the strain rate. Lu [
2] confirmed this conclusion. However, when in the cold liquid phase, Zr
41.2Ti1
3.8Ni
10Cu
20Be
22.5 also exhibits strain-rate-sensitive mechanical properties. The bulk amorphous alloys Zr
57Ti
5Ni
8Cu
20Al
10 [
3] and Pd
40Ni
40P
20 [
4] have been found to have a negative effect on the mechanical properties of strain rate; that is, increased strain rate, the strength of the material increases. In contrast, the strain rate of bulk amorphous alloys Nd
60Fe
20Co
10Al
10 [
5], Zr
25Ti
40Ni
8Cu
9Be
18 [
6], and Zr
16Ti
45Ni
9Cu
10Be
20 [
7] has a positive effect on their mechanical properties. Therefore, owing to the influence of various factors, such as the composition of the amorphous alloy, a general conclusion often cannot be drawn about the strain rate effect; therefore, the relevant mechanical properties of the amorphous alloy used in the study should be investigated. The three-dimensional, finite-deformation-based constitutive equations for metallic glasses developed by Thamburaja and Ekambaram [
8] have been proven capable of accurately recording the deformation behavior of amorphous alloys, such as Pd-based amorphous alloy and La61:4Al15:9Ni11:35Cu11:35 bulk metallic glass.
In the context of the application of amorphous material liners, Zheng [
9] proposed W-Cu-Zr non-metallic liner materials. Based on research on the comprehensive mechanical properties of this material, it was assumed that its use as liner material was conducive to improving the penetration power of warheads. Walters and Kecskes [
10] studied the jet formation and penetration of metal-glass shaped charge liners, demonstrating that the jet mainly presented a high-speed particle flow pattern composed of a large number of particles. The movements of high-speed particles were independent of each other, and the particles had certain radial velocities. When the blasting height was 2.3 times the diameter of the charge, an opening effect 0.51 times the diameter of the charge could be achieved. However, no detailed studies have been conducted on the specific formation process, the formation mechanism of the jet formed by the amorphous alloy hood, or the penetration model of the high-speed technical particle flow.
In this study, Zr41.2Ti13.8Cu12.5Ni10Be22.5 amorphous alloy material was taken as the research object. First, the dynamic mechanical properties of the material and the damage characteristics of the material under impact were analyzed. The formation process and characteristics of high-speed particle flow were analyzed in depth under explosive driving when the Zr41.2Ti13.8Cu12.5Ni10Be22.5 amorphous alloy material was used as the liner material. The results reported herein can provide technical guidance with respect to the selection of new materials suitable for shaped charge liners of shaped charge assault warheads, as well as technical support for the design of high-speed particle jet warheads.
4. Numerical Simulation of Jet Formation
A Ø56 mm standard shaped charge was modeled in this study. The charge had a height of 73.3 mm with a 1 mm thick Zr
41.2Ti
13.8Cu
12.5Ni
10Be
22.5 cone liner and a JH2 explosive with a density of 1.72 g/cm
3. The charge was detonated by a #8 detonator. The charge structure and the simulation model are shown in
Figure 10. In the simulation, the smoothed particle hydrodynamics (SPH) model was used in Autodyn 3D in ANSYS 17.1(ANSYS, Canonsburg, PA, USA).
The Zr-based amorphous alloy was described by the Johnson–Holmquist strength model and failure model and a polynomial state equation. The parameters of the Zr-based amorphous alloy and the JH2 explosive are shown in
Table 4 and
Table 5, respectively.
The Zr-based amorphous alloy jet formation and stretching process are shown in
Figure 11.
The jet tip velocity was 7252 m/s. At 60 µs, the continuity of the Zr-based jet was still good, and there was no necking phenomenon. The diameter of the Zr-based jet head increased continuously, showing incohesion characteristics. At 60 µs, the head diameter of the Zr-based jet reached 24.2 mm.
Chou et al. [
12] studied the plane axisymmetric collision mechanism, and the flow formation criteria were determined as follows. When a subsonic collision occurred, a dense, condensed jet always formed. When a supersonic collision occurred, there was a maximum angle (
) for the formation of an attached shockwave. When the collapse angle (
) was greater than
, an incohesion jet formed, and when the collapse angle (
) was less than
, a jet was formed. The bulk sound velocity of the Zr-based amorphous alloy was 5824 m/s, far exceeding the crushing velocity of approximately 4000 m/s. Thus, the requirements of the sound velocity criterion for incohesion jets formed by traditional metal materials were not met. Therefore, the expansion characteristics of the Zr-based amorphous alloy jet heads were not affected by the sound velocity criterion, demonstrating that the jet properties of the Zr-based amorphous alloy differed from those of conventional metal jets.
The particle density distribution at 30 µs is shown in
Figure 12 based on the mass and density distribution of the Zr-based jet,. For the Zr-based jet, aside from the core part of the jet, the density of which was still above 5.6 g/cm
3 at 30 µs, the outer density of the jet was generally low. The density was about 5.1 g/cm
3, the density variation range was 91.7%, and the density distribution gradually increased from the external surface to the core. The Zr-based jet exhibited no necking phenomenon, the diameter of the main body of the jet remained basically unchanged, and the microelements of the head material were in a state of force equilibrium. The Zr-based jet was a high-speed particle flow.
A high-speed particle flow is a kind of jet that cannot form a condensed jet and slug due to the influence of the mechanical properties of the liner material during the collapse process of the liner, instead forming a high-speed particle beam state containing most of the mass. When the particle flow formed by the Zr-based jet collapse converged at the impact point, mass redistribution occurred after a large number of high-speed particles were impacted. Particles with a high density were less affected by radial forces, and the radial velocity was low inside the jet. The particles with a low density were significantly affected by the radial force and had a high radial velocity outside the jet. Furthermore, owing to the high brittleness of the material itself, some low-density particles were broken under heavy loading, which increased the density range.
5. Results and Discussion
5.1. Fracture Behavior of Zr-Based Amorphous Alloy
After experimentation, fragments of irregular size and shape were obtained. The tungsten carbide shims had partially melted small fragments that were peeled off and appeared together with the fragments recovered in the collection device. The fracture angles of the larger fragments were measured and found to be less than 45°. However, according to the Tresca criterion, the Zr-based amorphous alloy should be shear-fractured on the plane of maximum shear stress (that is, the shear fracture angle should be 45°). This difference was due to the extremely high fracture strengths of Zr-based amorphous alloys, which produced high normal stresses on the shear sections, which inhibited the development of shear fractures. This results in a shear fracture angle smaller than the maximum shear stress surface, indicating that the composition of the Zr-based amorphous alloy obeyed the Mohr–Coulomb criterion. The fracture surfaces of the specimens were observed by SEM, and the fracture morphologies are shown in
Figure 13. Owing to the excessive number of fragments formed in the specimen, the local fracture morphology was selected to analyze the overall fracture morphology characteristics. Typical vein-like patterns were evident, but the Zr-based amorphous melting and droplet morphology were not evident near the vein pattern and in the crack propagation zone. The molten droplet was a result of the low thermal conductivity of the metallic glass and the high elastic strain. The elastic strain energy was high and released during local adiabatic shear, and the temperature in the shear band rose sharply to the glass phase-transition temperature or even close to the melting point temperature Tg of the material. The Tg of this Zr-based amorphous alloy was 932 K. The lack of molten droplets in the shear band may have been caused by the lack of structural defects of crystalline materials in the Zr-based amorphous alloy, the shear band not being fully developed during dynamic loading, the uneven elastic strain energy distribution, and the adiabatic shear fracture process first occurring in the local cluster structure with a partial stress concentration. Typical cleavage steps and accompanying river-like patterns are evident in
Figure 13a,b, which are microscopic morphological characteristics that are unique to brittle cleavage fractures under dynamic shock. In the quasi-static tests, the loading rate was low, and the specimen required a long time to complete the shear compensation and the formation and propagation of secondary shear bands. In the dynamic test, the shear band did not form and develop sufficiently under dynamic conditions because the loading rate was much higher than that in the static state, and there was not sufficient time to complete the shear compensation, resulting in fewer secondary shear bands. This explains the experimental phenomenon of smaller fracture strains of the Zr-based amorphous alloy specimens under the room temperature dynamic tests than those under room-temperature quasi-static tests, as well as the more evident brittleness.
5.2. Results of X-ray Test, Theoretical Calculation, and Simulation of Jet Formation
According to the analysis presented
Figure 14, 30 µs after initiation, the jet profile was clear, and the shape of each part of the jet can be clearly observed. The Zr-based jet exhibited satisfactory overall cohesiveness, with a slight expansion of the head and good continuity and symmetry of the whole jet. The image taken 60 µs after initiation shows that the overall continuity of the jet formed in the two tests was good, without necking, and the symmetry deteriorated. The overall edge of the jet was slightly fuzzy, resembling atomization, and the tail shape of the jet was significantly atomized. A comparison of the two time nodes showed that there was a transition section at the junction of the jet tail and the slug, with no evidence of morphological change. A collapse ring similar to the copper jet was not observed, but the particle swarm similar to the planetary belt was replaced because there was little effective charge at the bottom of the shaped charge liner, and the residual energy after crushing the liner was not sufficient to provide the particles with a high crushing speed. It was too late for the particles to converge to the axis, resulting in the bottom particle swarm flying around the high-speed particle flow. The above experimental phenomena are further proof that the jet existed in the form of a large number of high-speed particle flows, and a certain radial velocity was generated when the collision occurred, making the jet divergent.
A comparison of the pulsed X-ray photographs and the numerical simulation results shows that the appearances of the two were very close at the two times points, indicating that the SPH method could better describe the high-speed particle flow and the condensed jet and that the process was universal. Combined with the measurement data presented in
Table 3 and
Table 6, the simulated and measured values of the jet head velocity, head diameter, and jet length were in agreement, indicating the authenticity and reliability of the numerical simulation within this duration. For the Zr-based jet image, when
t = 30 µs, the jet formation time was short, the radial travel of the edge particles was small, and the jet had not diverged significantly. When
t = 60 µs, with the continuous movement of the particle flow, the low-density particles at the edge produced high displacement, and the atomization phenomenon was evident. In the numerical simulation, the main body of the jet showed no evident divergence, except at the head, possibly because the numerical simulation was more ideal than the experiment in calculating the process of the shaped charge liner crushing into particles. In the actual test, the particles crushed on the same circumference could not be guaranteed to have the same mass, causing variation in the radial velocities of particles, owing to differing momentum when the axis converged and collided, leading to the divergence of the main jet. Despite differences in the morphology, the relevant parameters of the Zr-based jet were still very close to the numerical simulation results. Thus, the numerical simulation can accurately simulate the formation performance of the jet within a certain range, and the data obtained from the numerical simulation can be used for analysis.
The theoretical calculation of the high-speed particle flow velocity formed by each microelement of the Zr-based amorphous alloy liner busbar under this working condition showed that the maximum velocity was 7298 m/s, which was 2.1% higher than the average particle flow velocity of the two tests. This was the result of only considering the elastic strain energy as the crushing energy, which reduced the total energy and increased the kinetic energy obtained by the particle flow. The theoretical model error was small, and it can be used to estimate the maximum velocity of the high-speed particle flow.
5.3. Result of DOP Test and Theorical Calculation of Jet Penetrate C35 Concrete
Two Zr-based amorphous alloy shaped charge DOP tests and one Cu shaped charge DOP test were conducted for comparison. The penetration and collapse of the shaped charge liner into the C35 concrete are shown in
Figure 15, and the measured test data are shown in
Table 7.
The crater diameter of the Cu shaped charge was about 180 mm (3.2 times the charging diameter), the depth of the funnel crater was 56 mm (equal to the charging diameter), the hole diameter (after the cleaning of the collapsed fragments) was about 25 mm (0.45 times the charging diameter), and the penetration depth (including the depth of the funnel crater) was 425 mm (7.59 times the charging diameter).
The average funnel crater diameter of the Zr-based amorphous alloy shaped charge was about 325 mm (5.8 times the charging diameter), the average depth of the funnel crater was 70 mm (1.25 times the charging diameter), the average hole diameter (after the cleaning of the collapsed fragments) was about 38 mm (0.68 times the charging diameter), and the average penetration depth (including the depth of the funnel crater) was 291.5 mm (5.2 times the charging diameter). Because the collapsed crater was deeper in the second test, the diameter of the entrance hole was slightly reduced. Moreover, the difference in the penetration depth was due to the concrete material characteristics, which caused the wall of the penetration hole to break and blocked the hole when it was penetrated. The penetration effects of the two tests were similar within a reasonable error range, indicating that the high-speed particle flow formed by the Zr-based amorphous alloy liner was relatively stable.
According to the above analysis, it can be concluded that although the penetration ability of the ZR-based shaped charge is less than that of the copper shaped charge (about 1.6 times that of copper), the ZR-based shaped charge achieves excellent performs in terms of hole-expanding ability, forming a large caving area and penetration hole size in the process of penetrating concrete.
A comparison of the theoretical and numerical simulation results with the experimental data are shown in
Table 8.
A comparison of the theoretical model with the experimental data showed that, in addition to the collapse funnel crater (which is difficult to obtain by calculations owing to the influence of the concrete material properties, the unavoidable accumulation area at the bottom of the hole, and the penetration of the hole wall in the test), the blockage caused by crushing reduced the penetration depth smaller in the test measurement. The error of the theoretically calculated hole diameter of the collapse crater bottom was 5.56%, and the error of the penetration depth was 6.45%. The errors of the hole diameter and penetration depth at the bottom of the collapse crater were within a reasonable range.