Journal of CeramicsVolume 2014 (2014), Article ID 618154, 6 pageshttp://dx.doi.org/10.1155/2014/618154

Research Article

Alumina-Based Ceramics for Armor Application: Mechanical Characterization and Ballistic Testing

M. V. Silva,¹ D. Stainer,² H. A. Al-Qureshi,¹ O. R. K. Montedo,³ and D. Hotza¹

¹Núcleo de Pesquisa em Materiais Cerâmicos e Vítreos (CERMAT), Programa de Pós-Graduação em Ciência e Engenharia de Materiais (PGMAT), Universidade Federal de Santa Catarina (UFSC), 88040-900 Florianópolis, SC, Brazil²CMC Tecnologia, Avenida Roberto Galli 1220, 88845-000 Cocal do Sul, SC, Brazil³Programa de Pós-Graduação em Ciência e Engenharia de Materiais (PPGCEM), Laboratório de Cerâmica Técnica (CerTec), Universidade do Extremo Sul Catarinense (UNESC), Avenida Universitária, 1105, 88806-000 Criciúma, SC, Brazil

Received 28 October 2013; Accepted 15 December 2013; Published 9 January 2014

Academic Editor: Shaomin Liu

Copyright © 2014 M. V. Silva et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

The aim of this work is to present results of mechanical characterization and ballistic test of alumina-based armor plates. Three compositions (92, 96, and 99 wt% Al₂O₃) were tested for 10 mm thick plates processed in an industrial plant. Samples were pressed at 110 MPa and sintered at 1600°C for 6 h. Relative density, Vickers hardness, and four-point flexural strength measurements of samples after sintering were performed. Results showed that the strength values ranged from 210 to 300 MPa depending on the porosity, with lower standard deviation for the 92 wt% Al₂O₃ sample. Plates (120 mm × 120 mm × 12 mm) of this composition were selected for ballistic testing according to AISI 1045, using a metallic plate as backing and witness plates in the case of penetration or deformation. Standard NIJ-0108.01 was followed in regard to the type of projectile to be used (7.62 × 51 AP, Level IV, 4068 J). Five alumina plates were used in the ballistic tests (one shot per plate). None of the five shots penetrated or even deformed the metal sheet, showing that the composition containing 92 wt% Al₂O₃ could be considered to be a potential ballistic ceramic, being able to withstand impacts with more than 4000 J of kinetic energy.

1. Introduction

Ceramics have been considered one of the most important materials for lightweight armor applications due to their low density, high compressive strength, and high hardness [1]. Ceramic materials for using as ballistic armor must be sufficiently rigid to fragment the bullet and reduce its speed, transforming it into small fragments that should be stopped by the layer of flexible material that supports the ceramic. Thus, it is necessary that the ceramic material presents high elastic modulus and high hardness [2]. Fracture toughness is also a very important requirement for this application.

The main ceramic materials used commercially in the development of ballistic armors are Al₂O₃, B₄C, SiC, and ceramic matrix composites (CMCs) such as Al₂O₃/ZrO₂ system. High cost, processing hindrances, and restrictions to predict ballistic performance from the properties of the material are some drawbacks of ceramic armors [3].

Alumina provides the best cost-benefit ratio among advanced ceramics, featuring high modulus of elasticity, high refractoriness, high hardness, and relatively lower cost. However, because of its low fracture toughness and low flexural strength, ballistic performance of alumina is lower when compared to SiC and B₄C [4]. The properties of the alumina may be improved, either by introducing zirconia or by the manufacturing CMCs, which increase fracture toughness and flexural strength by introducing tetragonal zirconia particles or ceramic fibers, respectively [5, 6].

Thus, ceramic materials are usually a part of a ballistic personal or vehicle protection system. Even in this case, only with a rigorous control of the microstructure assured a reliable ballistic performance can be. For example, a system consisting of a composite of B₄C and glass fibers or aramid fibers coated with a protective fabric is often used. The replacement of metallic materials by ceramic materials in armored vehicles may lead to weight reduction, autonomy increase, and higher level of protection [7].

A ballistic armor system consists of several layers. The first layer is usually formed of ceramic materials whose function is to cushion the initial impact of the projectile. This layer must fracture the tip of the projectile dissipating much of the kinetic energy of the projectile fragment mass and improve the distribution of impact pressure on the second layer. The second layer is also called backing and is formed of ductile materials. Its function is to absorb the kinetic energy of the fragments derived from the residual projectile and ceramics by plastic deformation [8]. The most important requirement of the backing is no fail during the initial stages of the penetration process of the projectile, that is, the backing must withstand compressive stresses transferred to the ceramic after impact. Thus, it would prevent the penetration of the shrapnel containing high kinetic energy and would not deform excessively, as this would jeopardize the lives of persons protected by the armor or the integrity of the equipment. It is important to mention that impacts at high speeds (high kinetic energies) are high complexity phenomena that present limited reproduction, because parameters such as the incidence of the projectile on the armor, for example, are extremely difficult to be adjusted or prevented [9].

The design of an armor using ceramic materials should consider that the fracture is associated with instantaneous loads in ballistic impacts, which are quite different from those associated with static loads. In static load condition, stresses and strains are distributed throughout the body subjected to the impact and all points are involved in the start of fracture. In the instantaneous loads, stresses and strains are very well localized, so that fractures may occur in an isolated part of the body. This kind of change can dramatically affect the mechanical properties of the material due to the high pressures and loading rates. The impact of high kinetic energy projectiles on the ceramic composite armor usually gives rise to a cone of fractures with radial and circumferential cracks [7].

Projectiles fired over alumina targets, whose tips were flattened, presented higher residual speeds after drilling the targets and therefore greater power of penetration in relation to projectiles with sharp geometry. Moreover, a single layer of ceramic material absorbs more energy than several layers with the same overall thickness [10]. In this case, immediately after the impact on the first plate occurs the formation of an axial crack in the interface between the plates, which causes premature fracture of the assembly. During the first stage of the mechanism of penetration, the most important factor is to keep the integrity of the ceramic so that it can erode the greatest possible amount of mass of the projectile, that is, delaying the startup of the fracture of the ceramic material. This factor is decisive for the choice of the ceramic material to be used.

It is not possible to ensure an effective correlation between ballistic performance and a single characteristic or property of the material, due to the dynamic nature of the event occurring at intervals of time ranging from nano- to microseconds. Thus, ballistic tests under certain conditions are always required to determine the effectiveness of the protection systems. The development of ceramic ballistic requires careful assessment of physical and mechanical properties of the material in order to obtain adequate performance ballistic plates to the level of protection required.

The aim of this work is to characterize alumina-based ballistic plates and to evaluate their performance in situations where high levels of kinetic energy are required.

2. Materials and Methods

Three alumina compositions were used in this study according to Table 1 (X-ray fluorescence spectrometry, (XRF), Philips PW 2400, The Netherlands). The mean particle sizes were determined using a laser scattering particle size analyzer (CILAS 1064L, France). Each composition was uniaxially compacted at 110 MPa into 120 mm × 120 mm × 10 mm plates in an industrial press (Sacmi PH-300, Italy), resulting in samples presenting an apparent density of  gcm⁻³. The specimens were then sintered at °C for 6 h (holding time) in an industrial kiln (2°Cmin⁻¹ heating rate). After cooling down to room temperature, crystalline phases developed during heat treatment of the bodies were determined in a X-ray diffractometry (Phillips X’Pert, The Netherlands) using CuK radiation, within a range of 5 to 100°. The theoretical densities (, gcm⁻³) of the sintered samples (using powdered pieces of the samples) were measured by He-pycnometry (AccuPyc 1330, Micromeritics, USA). The apparent density (, gcm⁻³) was determined by the Archimedes’ principle by water immersion at 20°C. The relative density () was calculated from the relationship between apparent density and theoretical density according to (1), while porosity was calculated from (2): Microhardness measurements were performed with a Vickers automatic hardness tester (Shimadzu HMV, Japan) equipped with a diamond Vickers indenter. Tests were carried out with load of 1 kg, according to Karandikar [3], for tests in ballistic ceramics. Each sample was polished for leveling surface, and submitted at least to 5 measurements. The bending strength () of the sintered samples was determined in a test machine (Model DL 2000, EMIC, Brazil), which consisted of a four-point test on thirty samples with dimensions of 100 mm × 15 mm × 10 mm at a load rate of 0.5 mmmin⁻¹. Weibull distribution [11] was used to evaluate the reliability of the obtained results and also to select the composition for the ballistic testing, according to the following for the cumulative probability of fracture: where is probability of fracture; is tested amount of material; is standard amount; is Weibull modulus; is tensile strength of the material; is parameter adjustment; is strength below which the fracture probability is zero.

Table 1: Chemical composition of the alumina used in this study (wt%).

Composition
Al₂O₃
SiO₂
CaO
MgO
Na₂O
Fe₂O₃

A92
92.0
2.5
2.3
2.8
0.1
0.03

A96
96.0
3.1
0.1
0.6
0.1
0.04

A99
99.7
0.0
0.0
0.1
0.1
0.02

Considering a constant amount of specimens, (4) can be applied for a given sampling: where , , and are known as Weibull parameters. The determination of those parameters is carried out considering firstly and then modifying the equation into the following expression: By using the linear regression method it is possible to determine the values of the parameters and .

Samples of sintered alumina (92 wt% Al₂O₃, 120 mm × 120 mm × 12 mm) were fixed in metal plates (backing, 120 mm × 120 mm × 4 mm) of SAE 1045 steel for the ballistic tests. A metal substrate was also designed to engage and support the specimen during the impact of the shot as shown in Figure 1.

(a)

(b)

Figure 1: Schematic pictures of the test stand: (a) metallic substrate of the specimens; (b) specimens inserted into the metallic support.

There are two main international standards used to evaluate the performance of ballistic protection: NIJ-0101.04 and NIJ-0108.0 (National Institute of Justice) [12] and NATO (North Atlantic Treaty Organization) STANAG 4569 [13]. Tables 2 and 3 show test parameters for ballistic materials resistant to projectiles at different levels of ballistic protection, respectively for standards, NIJ-0108.01 and STANAG 4569. The ballistic testing was carried out based on the standards with the following modifications: a Mauser M1908 riffle with 7.62 AP bullets (STANAG III/NIJ IV) was used in the tests made at 15 m of distance with one shot per panel. Polyurethane webs of approximately 3 mm thickness were placed in front of ceramic plates to retain fragments of the projectile and the ceramic released during the test. A backing plate was used as control.

Table 2: Standard NIJ-0108.01 test parameters for ballistic materials resistant to projectiles at different levels of ballistic protection.

Level of ballistic protection
Ammunition type
Nominal mass (g)
Barrel length (cm)
Projectile velocity (m/s)
Kinetic energy (J)
Shots per panel

I
.22 LRHV Lead
2.6
15–16.5
320 ± 12
133.12
5

.38 Special RN Lead
10.2
15–16.5
259 ± 15
342.12

II-A
9 mm FMJ
10.2
10–12
381 ± 12
440.09
5

.357 Mag JSP
8.0
10–12
332 ± 12
740

II
9 mm FJM
10.2
15–16.5
425 ± 15
512.66
5

.357 Mag JSP
8.0
10–12
358 ± 12
921

III-A
44 Magnum Lead SWC
15.55
14–16
426 ± 15
725.9
5

9 mm FMJ
8.0
24–26
426 ± 15
1406

III
7.62 × 51 FJNB
9.7
56
838 ± 15
3405
5

308 Winchester FMJ

IV
30-06 AP
10.8
56
868 ± 15
4068.5
1

Table 3: Standard STANAG 4569 test parameters for armored vehicles at different levels of ballistic protection.

Level of ballistic protection
Threat
Ammunition type
Test distance (m)
Projectile velocity (±15 m/s)

I
Rifle
7.62 × 51 NATO Ball (Ball M80)
30
833

5.56 × 45 NATO SS109
900

5.56 × 45 M193
937

II
Infantry rifle
7.62 × 39 APIBZ
30
695

III
Sniper rifle
7.62 × 51 AP ( WC core)
30
930

7.62 × 54 R B32 API (Dragunov)
30
854

IV
Heavy machine gun
14.5 × 114 AP/832
200
911

V
Automatic cannon
25 mm APDS-TM-791 or TLB 073
500
1258

3. Results and Discussion

Figure 2 shows the XRD patterns of the used compositions. As expected, the sintered samples were mostly constituted by -Al₂O₃ (JCPDS 10-0173). However, diffraction pattern of composition A92 showed the following minority crystalline phases: spinel (MgAl₂O₄), wollastonite (CaSiO₃) and hibonite (CaAl₁₂O₁₉). These phases were formed due to the sintering additives employed.

Figure 2: XRD patterns of the used compositions: (a) A92, (b) A96, and (c) A99. C: -Al₂O₃ (JCPDS card n. 10-0173).

Figure 3 shows the particle size distribution of the used compositions. As it can be seen, those materials present a practically monomodal distribution, with mean particle size () of 2.92, 2.41, and 4.10 μm, respectively, for A92, A96, and A99.

Figure 3: Particle size distribution of the used compositions: (a) A92, (b) A96, and (c) A99.

Table 4 shows values of relative density and porosity of the sintered compositions. Relative densities were found to be around 97-98%. As expected, relative density decreased with increasing -Al₂O₃ contents, for the same forming pressure, sintering temperature, and holding time. Moreover, mean particle size of composition A99 was higher than the other ones that should have caused less accommodation of the particles and consequently more porosity compacts.

Table 4: Apparent density, theoretical density, relative density, and porosity of the sintered compositions.

Composition
A92
A96
A99

Apparent density (, g·cm⁻³)
3.65 ± 0.01
3.70 ± 0.01
3.85 ± 0.02

Theoretical density (, g·cm⁻³)
3.70 ± 0.01
3.80 ± 0.01
3.96 ± 0.01

Relative density (, %)
98.7
97.6
97.1

Porosity (ε, %)
1.3
2.4
2.9

Table 5 shows values of Vickers hardness of sintered compositions. Despite of differences in porosity, the investigated compositions showed values of Vickers hardness above 14 GPa in good agreement with values obtained by Karandikar [3] for commercial ballistic ceramics. Hardness is a very important mechanical property for ballistic application since it is expected the rupture of the projectile by the ballistic plate.

Table 5: Vickers hardness of sintered compositions.

Compositions
HV (GPa)

A92
14.8 ± 0.6

A96
13.3 ± 0.9

A99
14.8 ± 0.7

Table 6 shows values of bending strength and Weibull modulus for the studied compositions. All compositions presented similar values of bending strength considering the standard deviations presented. Nevertheless, compositions A92 and A99 showed practically the same average values of bending strength, which are higher than the ones for composition A96. This can be statistically confirmed with a 95% of confidence level by the analysis of variance and hypothesis test, as shown in Tables 7 and 8, and Figure 4.

Table 6: Bending strength () and Weibull modulus () for the tested compositions.

Composition
A92
A96
A99

(MPa)
221 ± 40
195 ± 40
227 ± 20

(MPa)
225
201
231

6.4
4.8
8.0

Table 7: Results of statistical hypothesis test.

Linear hypotheses
Estimate
SD Error
T value
Pr ()

96-10–92-10
29.676
10.973
−2.704
0.0223

99-10–92-10
1.647
10.973
0.150
0.9877

99-10–96-10
31.323
10.681
2.933
0.0120

Table 8: Results of the analysis of variance.

Linear hypotheses
Estimate
Lower
Upper

96-10–92-10
−29.6763
−55.8574
−3.4952

99-10–92-10
1.6465
−24.5346
27.8276

99-10–96-10
31.3229
5.8401
56.8056

Figure 4: Analysis of variance (ANOVA) for a factor.

Moreover, composition A96 showed a very lower value of in comparison with compositions A92 and A99 for a technical application. In fact, technical ceramics must show values of ranging from 5 to 10 according to Kanno [14]. In this sense and considering the value of , composition A96 could not be used for ballistic tests. On the other hand, compositions A92 and A99 showed suitable values of for technical application and there is no statistical evidence of significant difference between them, as shown by their linear function. However, because of its lower porosity, composition A92 was selected for ballistic tests.

Figures 5 and 6 show the results of the shots on the ballistic plates prepared from composition A92. In fact, a high amount of energy was absorbed by the alumina plate causing its fracture. Nevertheless, its hardness caused the breaking of the projectile into small fragments. Fragments did not penetrate or cause deformation in none of the backing (metallic plates) of the five plates tested. The velocity of the projectile in the impact was estimated to be ~865 ms⁻¹, while the kinetic energy should be above 4000 J. In this way, all the tested plates were approved in the ballistic tests (Level IV of Standard NIJ-0108.01). Those results are in very good agreement with those obtained by Karandikar [3] (alumina, 10 mm thickness) and above to those obtained by Couto [7] (level III, alumina/zirconia, 11.3 mm thickness).

(a)

(b)

(c)

Figure 5: Results of the shots carried out on the ballistic plates prepared from composition A92: (a) front view before impact, (b) front view after the impact of the projectile 7.62 × 51 AP, and (c) a detail of the local impact of the projectile on the surface of alumina after removing of the fragments.

Figure 6: View of the hole caused by the shot over the plate of polyurethane.

4. Conclusion

Three compositions of commercial alumina containing 92, 96, and 99.7 wt% Al2O3, named compositions A92, A96, and A99, respectively, were investigated in this work to be used as ballistic ceramics. Compositions were characterized by Vickers hardness measurements and four point flexural bending strength. The reliability of the obtained results was evaluated by Weibull statistics. According to the obtained results, one composition was selected for the ballistic testing. Compositions A92 and A99 showed comparable results with each other and higher Vickers hardness and bending strength than composition A96; however, composition A92 was selected for ballistic tests because of its lower porosity. Alumina plates (12 mm thickness) were submitted to a procedure based on the Standard NIJ-0108.01 (Level IV, 865 ms⁻¹, more than 4000 J). Fragments did not penetrate or cause deformation in none of the backing (metallic plates) of the five plates tested. All the tested plates were approved in the ballistic tests.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgment

The authors are grateful to Coordenação de Aperfeiçoamento de Pessoal de Nível Superior (CAPES/Brazil) for funding this work.

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