Characterization and Consolidation of Tungsten 

Nanopowders Produced by Salt-Assisted 

 Combustion Synthesis 

by Bradley R. Klotz, Franklyn R. Kellogg, and Kyu C. Cho 

ARL-TR-5311 September 2010 

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Army Research Laboratory 

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ARL-TR-5311 September 2010 

Characterization and Consolidation of Tungsten 

Nanopowders Produced by Salt-Assisted 

 Combustion Synthesis 

Bradley R. Klotz

Dynamic Science, Inc. 

Franklyn R. Kellogg

Data Matrix Solutions 

Kyu C. Cho 

Weapons and Materials Research Directorate, ARL

Approved for public release; distribution is unlimited. 
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Characterization and Consolidation of Tungsten Nanopowders Produced by SaltAssisted Combustion Synthesis 

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Bradley R. Klotz, Franklyn R. Kellogg†, and Kyu C. Cho 

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14. ABSTRACT 

Tungsten nanopowders have been produced at Chungnam National University in Daejeon, South Korea, by a salt-assisted 

combustion synthesis method. Samples of these powders were obtained and characterized to determine particle size, 

morphology, degree of agglomeration, and chemical purity. The powders were shown to consist of nano-sized particles 

agglomerated into larger clusters and were found to contain higher levels of oxygen than conventional fine tungsten powder. 

The powders were then consolidated by the Plasma Pressure Compaction (P2

C) method. The resulting samples were examined 

to determine density, grain size, and chemical purity. Although bulk samples were produced containing nano-sized grains, high 

density was not achieved. However, when compared with samples consolidated using conventional sub-micron tungsten 

powder, higher density was achieved at the lower processing temperatures required for retention of initial grain size. 

15. SUBJECT TERMS

tungsten, nanopowder, plasma pressure compaction 

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Bradley R. Klotz 

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iii

Contents 

Contents iii

List of Figures iv

List of Tables v

1. Introduction 1

1.1 Objective .........................................................................................................................1

1.2 Background .....................................................................................................................1

2. Experimental Procedure 2

3. Results and Discussion 4

3.1 Powder Characterization .................................................................................................4

4. Conclusions 20

5. References 21

Distribution List 23 
iv

List of Figures 

Figure 1. Schematic of the P2C apparatus. ......................................................................................3

Figure 2. FESEM micrographs of CNU tungsten powder no. 1. ....................................................5

Figure 3. FESEM micrographs of CNU tungsten powder no. 2. ....................................................6

Figure 4. FESEM micrographs of CNU tungsten powder no. 3. ....................................................7

Figure 5. FESEM micrographs of CNU tungsten powder no. 14. ..................................................8

Figure 6. FESEM images of Osram Sylvania M-10 tungsten powder. ..........................................9

Figure 7. Particle size distribution plots for (a) CNU powder no. 1, (b) CNU powder no. 2, 

(c) CNU powder no. 3, and (d) CNU powder no. 14. ..............................................................10

Figure 8. X-ray diffraction patterns for (a) CNU tungsten powder no. 1, (b) CNU tungsten 

powder no. 2, (c) CNU tungsten powder no. 3, and (d) CNU tungsten powder no. 14. ..........12

Figure 9. FESEM micrographs of consolidated CNU tungsten powder no. 1. .............................15

Figure 10. FESEM micrographs of consolidated CNU tungsten powder no. 2. ...........................15

Figure 11. FESEM micrographs of consolidated CNU tungsten powder no. 3. ...........................16

Figure 12. FESEM micrographs of consolidated CNU tungsten powder no. 14. .........................16

Figure 13. X-ray diffraction patterns for consolidated samples of (a) powder no. 1, (b) 

powder no. 2, (c) powder no. 3, and (d) powder no. 14. ..........................................................17

Figure 14. FESEM micrographs of P2C consolidated M-10 tungsten with (a) no 

pretreatment, (b) hydrogen reduction, (c) pulsing, and (d) hydrogen reduction and 

pulsing. .....................................................................................................................................19

Figure 15. SEM micrograph of consolidated submicron tungsten powder showing retained 

initial grain size. .......................................................................................................................20
v

List of Tables 

Table 1. Powder data from CNU. ...................................................................................................2

Table 2. Carbon and oxygen analysis of CNU tungsten powder nos. 1, 2, and 3. ........................11

Table 3. Elemental analysis of CNU tungsten powder nos. 1 and 14. ..........................................11

Table 4. Densities of CNU tungsten P2C samples. .......................................................................14

Table 5. Densities of Osram Sylvania M-10 tungsten P2C samples. ............................................19
vi

INTENTIONALLY LEFT BLANK. 
1

1. Introduction 

1.1 Objective 

Researchers at Chungnam National University (CNU) in Daejeon, South Korea have used a saltassisted combustion synthesis method to synthesize tungsten nanopowders using a mixture of 

tungsten trioxide, zinc, and sodium chloride (WO3+Zn+NaCl). The following report details 

efforts to evaluate these tungsten powders for use in the consolidation of bulk nanocrystalline 

samples. Particle size, morphology, degree of agglomeration, and chemical purity of the starting 

powder were examined using a variety of powder characterization techniques. Consolidation of 

the powders was carried out by Plasma Pressure Compaction (P2

C). Resulting samples were 

examined to evaluate properties such as density, grain size, and chemical purity. Results were 

compared with those achieved for submicron-sized tungsten powder. 

1.2 Background 

Because of its high density, tungsten has been considered as a candidate material to replace 

depleted uranium (DU) in kinetic-energy penetrators. DU is currently used due to its high 

density, as well as its tendency to form adiabatic shear bands as the penetrator enters a target, 

resulting in a chiseled nose and increased penetration depth (1). It is tungsten’s resistance to this 

adiabatic shear localization that limits its applicability in anti-armor applications (2). Studies of 

nanocrystalline (<100 nm) and ultra-fine grain (UFG) (<300 nm) iron have shown that reducing 

the grain size of the material results in a tendency for deformation during quasi-static testing to 

occur by shear banding as opposed to the uniform deformation seen in conventional grain-sized 

iron (3). Moreover, recent studies have shown that when tungsten grains are refined to the 

nanocrystalline and ultra-fine grain (UFG) regime by severe plastic deformation techniques, 

reduced strain rate sensitivity and localized shearing are observed (4, 5). Thus, a penetrator 

made of nanocrystalline tungsten could possibly duplicate the performance of DU. 

The consolidation of nano-sized tungsten powder by a technique that will result in the retention 

of initial grain size is one method of producing bulk nanocrystalline parts. Properties of the 

starting powder, such as chemical purity, particle size, size distribution, morphology, and degree 

of agglomeration are important factors that determine the densification behavior of a powder. 

Thus, powder characterization is an important step prior to consolidation. Experiments have 

already been undertaken at the U.S. Army Research Laboratory (ARL) to consolidate fine-grained 

and nano-sized tungsten by the Plasma Pressure Compaction (P2

C) method (6, 7). The P2C 

method subjects powder in a graphite die to high current DC voltage, enabling rapid heating rates 

and very short high-temperature hold times. Submicron tungsten powder has been previously 

consolidated by P2

C to ~97% theoretical density (7). However, the high density of the 

consolidated samples came at the expense of grain growth, with final grain sizes approximately 
2

10 times the initial particle size. The use of nanocrystalline tungsten powders could provide for 

a sample with final grain size in the nanocrystalline regime. The study detailed in this report 

seeks to compare the powder characteristics and consolidation behavior of the CNU-produced 

nanocrystalline tungsten powders mentioned previously to those of conventional submicron 

tungsten powder. 

2. Experimental Procedure 

Four different grades of CNU-synthesized tungsten powder were selected for analysis and 

consolidation. The CNU powders were designated tungsten powder nos. 1, 2, 3, and 14. Powder 

data provided by CNU for each of the powders is shown in table 1. Powder nos. 1 and 2 were 

different lots of particles synthesized by the same method. Powder no. 3 was produced under 

slightly different conditions than the first two powders. Powder no. 14 was similar to powder no. 

1, but a secondary heat treatment was performed by CNU to reduce oxygen concentration in the 

final powder. Powder characteristics and consolidation data obtained previously for Osram 

Sylvania M10-grade tungsten powder (manufacturer specified particle size: 0.60–0.90 m) and 

Teledyne Wah Chang tungsten powder (manufacturer specified particle size: 0.70–0.99 m) 

were used for comparison with the nanopowders (6, 7). The size and morphology of the asreceived nanopowders were observed on a Hitachi S-4700 field emission scanning electron 

microscope (FESEM) with energy dispersive x-ray spectroscopy (EDS) capabilities. Samples of 

each powder were also dispersed in a water-glycerol mixture, and the particle size distribution 

(PSD) was determined by laser scattering techniques on a Horiba LA-910 Laser Scattering 

Particle Size Distribution Analyzer. Elemental chemical analysis of the powders was carried out 

by Luvak, Inc. of Boylston, MA. The amount of sulfur and carbon was determined by 

combustion infrared detection, oxygen content was measured by inert gas fusion, and all other 

elements were measured by direct current plasma emission spectroscopy. Powder nos. 1, 2, and 

3 were initially sent out for measurement of only carbon and oxygen content. A sample of 

powder no. 14 and an additional sample of powder no. 1 were also sent for measurement of a 

broader spectrum of elements to examine the difference that hydrogen heat treatment made in 

impurity content. In addition, an x-ray diffraction (XRD) pattern to detect the presence of 

impurity phases was generated for each powder on a Phillips x-ray diffractometer with Phillips 

X-Pert Analysis software. 

Table 1. Powder data from CNU. 

Powder Oxygen Content 

(weight-percent) 

Particle Size 

(nm) 

Quantity 

(kg) 

Tungsten no. 1 1.7 80–90 2.0 

Tungsten no. 2 1.7 100–110 0.25 

Tungsten no. 3 1.7 200 0.25 

Tungsten no. 14 0.25–0.3 80–120 1.4 
3

For the powders obtained from CNU, no treatment was performed at ARL prior to P2C 

consolidation. Each powder sample was consolidated in the as-received condition. The 

development of P2C processing parameters for tungsten has been described previously (6, 7). 

For this study, 50 g of the CNU tungsten powders were packed into 1-in-diameter graphite dies 

and placed between two water cooled platens in the chamber of the P2C apparatus (figure 1). 

Samples were loaded at a pressure of 27 MPa. Prior to consolidation, the chamber was pumped 

down to 10 mTorr or less. All consolidation runs were carried out under vacuum. The samples 

were first subjected to a pulsed current with 10 μs on/off times. Pulsing currents of 200, 400, 

600, 800, and 1000 A were applied in a step-wise fashion, with 5-min intervals at each pulsing 

step. The temperature of the sample was monitored at the outside surface of the die with an 

optical pyrometer, although the temperature inside the die is known to be much higher (8). The 

lowest temperature that the pyrometer was capable of reading was 636 °C. The pulsing 

parameters were run until the pyrometer began to register a temperature reading. For most 

samples, this occurred after being at 1000 A for 5 min. Once the pyrometer became active, the 

pressure was increased to 100 MPa, the power supply was switched to constant current mode, 

and the current was rapidly increased to 5000 A. The applied current of 5000 A was maintained 

until the sintering temperature was reached, at which point, the current was rapidly lowered to 0 

and the sample was allowed to cool under vacuum. 

Figure 1. Schematic of the P2C apparatus. 

Once removed from the P2C chamber, samples were ejected from the die and ground to remove 

graphite or tungsten carbide on the surface. Density was measured by the Archimedes’ method. 

Samples were then sectioned to provide samples for scanning electron microscopy and x-ray 

diffraction. 
4

3. Results and Discussion 

3.1 Powder Characterization 

FESEM micrographs of the four different grades of CNU tungsten nanopowders are shown in 

figures 2–5. Powder nos. 1 and 2 appeared similar, consisting of fine particles clustered in large 

agglomerates, some on the order of 10–20 m. The fine particles in these two powders looked to 

be less than 100 nm on average, and there appeared to be very little joining between the particles. 

The sample of powder no. 3 contained less large agglomerates, and the size of the fine particles 

appeared on the order of those seen in powder nos. 1 and 2. However, their appeared to be more 

joining between the fine particles in powder no. 3 than in the first two powders. Powder no. 14, 

which was the same grade as powder no. 1 but had been heat treated by CNU in hydrogen prior 

to sending to ARL, contained more large agglomerates than the other three powders, the largest 

being on the order of 50 m. There also appeared to be some sintering and coalescence of the 

fine particles as shown in the high magnification images, most likely as a result of the secondary 

heating cycle. For comparison purposes, FESEM micrographs of the Osram Sylvania M-10 

powder are shown in figure 6. 
5

Figure 2. FESEM micrographs of CNU tungsten powder no. 1. 
6

Figure 3. FESEM micrographs of CNU tungsten powder no. 2. 
7

Figure 4. FESEM micrographs of CNU tungsten powder no. 3. 
8

Figure 5. FESEM micrographs of CNU tungsten powder no. 14. 
9

Figure 6. FESEM images of Osram Sylvania M-10 tungsten powder. 

Particle size distribution plots, as generated on the Horiba LA-910 for each of the four CNU 

tungsten powders, are shown in figure 7. The LA-910 is able to detect a wide range of particle 

sizes, so it is able to distinguish the large agglomerates observed by FESEM. Particle sizes down 

to <100 nm can be seen in plots for powder nos. 1, 2, and 14. Powder nos. 3 and 14 appeared to 

show less fine particles, likely due to the joining between the particles seen in the FESEM 

micrographs. 

The results of chemical analysis of CNU powder nos. 1, 2, and 3 for measurement of carbon and 

oxygen are shown in table 2. The three powders showed consistent levels of both elements in 

each powder, with the oxygen level being higher than that measured by CNU. Elemental 

analysis for powder nos. 1 and 14 are shown in table 3. Powder no. 14, which underwent 

secondary heat treatment in hydrogen after synthesis, contained much less oxygen than powder 

no. 1, as well as lower levels of carbon and zinc. The Osram Sylvania M-10 tungsten powder 

was measured to contain 0.59 weight-percent oxygen, which is significantly lower than all but 

the hydrogen-reduced CNU powder no. 14. 
10

a)

b)

c)

d)

Figure 7. Particle size distribution plots for (a) CNU powder no. 1, (b) CNU powder no. 2, (c) CNU 

powder no. 3, and (d) CNU powder no. 14. 
11

Table 2. Carbon and oxygen analysis of CNU tungsten powder nos. 1, 2, and 3. 

Element Powder No. 1 

(weight-percent) 

Powder No. 2 

(weight-percent) 

Powder No. 3 

(weight-percent) 

Carbon 0.60 0.46 0.65 

Oxygen 2.42 2.38 2.34 

Table 3. Elemental analysis of CNU tungsten powder nos. 1 and 14. 

Element Tungsten Powder No. 1 

(weight-percent) 

Tungsten Powder No. 14 

(weight-percent) 

Ag 0.0005 0.0005 

Al 0.0005 0.0024 

As 0.0020 0.0020 

Bi 0.0020 0.0020 

C 0.0670 0.0250 

Ca 0.0005 0.0006 

Co 0.0005 0.0005 

Cr 0.0005 0.0005 

Cu 0.0037 0.0011 

Fe 0.0005 0.0010 

Mg 0.0005 0.0005 

Mo 0.0005 0.0005 

N 0.6600 0.0380 

Ni 0.0005 0.0005 

O 2.8000 0.3500 

P 0.0020 0.0020 

Pb 0.0780 0.0010 

S 0.0030 0.0020 

Sb 0.0020 0.0020 

Si 0.0030 0.0030 

Sn 0.0020 0.0020 

Ti 0.0005 0.0005 

V 0.0005 0.0005 

Zn 1.3100 0.5200 

Zr 0.0650 0.0170 

X-ray diffraction patterns for the four CNU tungsten powders are shown in figure 8. Powder 

nos. 1 and 2 appeared similar, with no significant peaks for phases other than tungsten visible. 

Powder no. 3 was seen to contain peaks for tungsten oxide. Powder no. 14, which had the lowest 

oxygen content as determined by chemical analysis, also did not show a significant amount of 

any phases other than tungsten. 
12

a)

b)

Figure 8. X-ray diffraction patterns for (a) CNU tungsten powder no. 1, (b) 

CNU tungsten powder no. 2, (c) CNU tungsten powder no. 3, and 

(d) CNU tungsten powder no. 14.
13

c)

d)

Figure 8. X-ray diffraction patterns for (a) CNU tungsten powder no. 1, (b) 

CNU tungsten powder no. 2, (c) CNU tungsten powder no. 3, and 

(d) CNU tungsten powder no. 14 (continued).
14

3.2 Powder Consolidation 

Based on the results of a previous study on consolidation of nano-scale tungsten powder (9), it 

was decided that a lower temperature would be used for P2

C consolidation of the four CNU 

tungsten powders in an attempt to retain initial grain size. Thus, all four CNU samples were 

consolidated with a final consolidation temperature of 1200 °C. No pre-treatment of the powders 

was done prior to consolidation. Densities of the four samples are shown in table 4. FESEM 

photos are shown in figures 9–12. 

Table 4. Densities of CNU tungsten P2C samples. 

Powder No. Consolidation Temperature

(oC) 

Density 

(g/cm3

) 

Theoretical Density 

(°) 

1 1200 14.73 76.3 

2 1200 15.27 79.1 

3 1200 15.57 80.7 

14 1200 15.06 78.0 

None of the consolidated samples of CNU powder were able to achieve full density at the 

temperature used. Despite the sample made with powder no. 2 having a slightly higher density 

when compared with the sample made with powder no. 1, the samples had similar 

microstructures as seen in the FESEM images in figures 9 and 10. The structure appeared 

irregular, with areas of higher density and areas containing porosity and oxide phases. The grain 

size for these two samples was similar. The sample made with powder no. 3 as shown in figure 

11 had a more uniform microstructure and a finer grain size than the previous two specimens, but 

also contained a large amount of porosity and oxide phases. The consolidated sample of powder 

no. 14 (figure 12) showed little or no oxide phases and had an irregular microstructure containing 

well-sintered areas and areas of porosity. The grain size of this sample was similar to that of the 

powder no. 3 sample. Figure 13 shows the XRD patterns for each of the consolidated samples. 

The samples from powder nos. 1, 2, and 3 now exhibit tungsten oxide (WO2) peaks, which were 

only evident prior to consolidation in powder no. 3. This oxide phase, which could be seen in 

the FESEM images, must have formed during consolidation due to the high oxygen content of 

the powders. The powder no. 14 sample, which used powder that underwent hydrogen reduction 

heat treatment to reduce the oxygen level, showed no significant oxide peaks. 
15

 

Figure 9. FESEM micrographs of consolidated CNU tungsten powder no. 1. 

 

Figure 10. FESEM micrographs of consolidated CNU tungsten powder no. 2. 
16

 

Figure 11. FESEM micrographs of consolidated CNU tungsten powder no. 3. 

Figure 12. FESEM micrographs of consolidated CNU tungsten powder no. 14. 
17

a)

b)

Figure 13. X-ray diffraction patterns for consolidated samples of (a) powder 

no. 1, (b) powder no. 2, (c) powder no. 3, and (d) powder no. 14.
18

c)

d)

Figure 13. X-ray diffraction patterns for consolidated samples of (a) powder 

no. 1, (b) powder no. 2, (c) powder no. 3, and (d) powder no. 14 

(continued). 
19

A previous study produced specimens of Osram Sylvania M-10 tungsten powder consolidated by 

P2

C at a temperature of 1700 oC and a pressure of 65 MPa using different powder treatments 

prior to consolidation (7). Powder pretreatment processes included hydrogen heat treatment of 

the powder in a graphite die before loading into the P2C chamber, and the application of pulsed 

current before the final consolidation step. Densities for the M-10 consolidated samples are 

shown in table 5. FESEM micrographs can be seen in figure 14. 

Table 5. Densities of Osram Sylvania M-10 tungsten P2C samples. 

Powder Pretreatment Density 

(g/cm3

) 

Theoretical Density 

(°) 

None 17.49 90.6 

Hydrogen reduction 18.28 94.7 

Pulsing 18.39 95.3 

Hydrogen reduction and pulsing 18.70 96.9 

a) b)

c) d)

Figure 14. FESEM micrographs of P2C consolidated M-10 tungsten with (a) no pretreatment, 

(b) hydrogen reduction, (c) pulsing, and (d) hydrogen reduction and pulsing. 
20

The consolidated M-10 tungsten samples can be compared with those produced using the CNU 

nanopowders. The sample of M-10 powder with the highest sintered density (96.9% theoretical) 

had a grain size on the order of 5–10 m. Processing of the CNU powders at lower temperatures 

resulted in samples with a grain size on the order of 500 nm. However, this retention of grain 

size came at the expense of sample density, as the highest density achieved for the CNU powder 

consolidated at 1200 oC was 80.7% theoretical. Another previous study on P2

C consolidation of 

tungsten showed that for a submicron tungsten powder with average particle size between 0.7 

and 0.99 m, initial grain size was retained using a lower consolidation temperature, but final 

density was only 66.3% theoretical (6). A sintered microstructure from this sample is shown in 

figure 15. A comparison with the present study shows that an advantage of using nanopowders 

is the ability to achieve higher densities at the lower processing temperatures required to retain 

initial grain size. 

Figure 15. SEM micrograph of 

consolidated submicron 

tungsten powder 

showing retained initial 

grain size. 

4. Conclusions 

The purpose of this report was to characterize and evaluate the consolidation behavior of 

nanocrystalline tungsten powders produced at the Chungnam National University in Daejon, 

South Korea. The powders were shown to consist of nano-sized particles clustered into larger 

agglomerates. The powders also were found to contain higher levels of oxygen than 

conventional fine tungsten powder. The oxygen content was able to be reduced by a heat 

treatment procedure performed after powder production. It was possible to produce bulk 

samples with nano-sized grains by the P2

C method, but high density samples were not achieved. 

However, when compared with samples consolidated using conventional submicron tungsten 

powder, use of the CNU nanopowders was able to produce samples with higher densities at the 

lower temperatures required to retain initial grain size. 
21

5. References 

1. Magness, L. S.; Farrand, T. G. Deformation Behavior and its Relationship to the Penetration 

Performance of High Density Kinetic Energy Penetrator Materials, Durham, NC, 

Proceedings of the 17th Army Science Conference, Durham, NC, 1990, pp 149–165. 

2. Cai, W. D.; Li, Y.; Dowding, R. J.; Mohamed, F. A.; Lavernia, E. J. A Review of TungstenBased Alloys as Kinetic Energy Penetrator Materials. Reviews in Particulate Materials

1995, 3, 71–132. 

3. Wei, Q.; Jia, D.; Ramesh, K. T.; Ma, E. Evolution and Microstructure of Shear Bands in 

Nanostructured Fe. Applied Physics Letters 2002, 81 (7), 1240–1242. 

4. Wei, Q.; Jiao, T.; Ramesh, K. T.; Ma, E.; Kecskes, L. J.; Magness, L.; Dowding, R.; 

Kazykhanov, V. U.; Valiev, R. Z. Mechanical Behavior and Dynamic Failure of HighStrength Ultrafine Grained Tungsten Under Uniaxial Compression. Acta Materialia 2006, 

54 (1), 77–87. 

5. Wei, Q.; Zhang, H. T.; Schuster, B.; Ramesh, K. T.; Ma, E.; Valiev, R. Z.; Kecskes, L. J.; 

Cho, K. C.; Dowding, R. J.; Magness, L. Microstructure and Mechanical Properties of 

Super-Strong Nanocrystalline Tungsten by High-Pressure Torsion. Acta Materialia 2006, 54

(15), 4079–4089. 

6. Cho, K.; Woodman, R.; Klotz, B.; Dowding, R. Plasma Pressure Compaction of Tungsten 

Powders. Materials and Manufacturing Processes 2004, 19 (4), 619–630. 

7. Cho, K.; Kellogg, F.; Klotz, B.; Dowding, R. Plasma Pressure Compaction (P2

C) of 

Submicron Size Tungsten Powder. Proceedings of the International Conference on 

Tungsten, Refractory, and Hardmetals VI, 2006. 

8. McWilliams, B.; Zavaliangos, A.; Cho, K. C.; Dowding, R. J. The Modeling of ElectricCurrent-Assisted Sintering to Produce Bulk Nanocrystalline Tungsten. JOM: Journal of the 

Minerals, Materials, and Metals Society 2006, 58 (4), 67–71. 

9. Klotz, B. R.; Kellogg, F. R.; Klier, E. M.; Dowding, R. J.; Cho, K. C. Characterization, 

Processing, and Consolidation of Nanoscale Tungsten Powder; ARL-TR-5045; U.S. Army 

Research Laboratory: Aberdeen Proving Ground, MD, 2009. 
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 R DARCY 

 R JOINSON 

 D RIGOGLIOSO 

 BLDG 354 

 PICATINNY ARSENAL NJ 07806-5000 

 1 US ARMY TARDEC 

 AMSRD TAR R 

 D TEMPLETON 

 6501 E 11 MILE RD 

 WARREN MI 48397-5000 

 1 US ARMY RDECOM 

 RDMR AEF T 

 J CHANG 

 BLDG 4488 RM B274 

 REDSTONE ARSENAL AL 35898 

 2 US ARMY RDECOM 

 RDMR AEF 

 G LIU 

 R MCFARLAND 

 BLDG 4488 

 REDSTONE ARSENAL AL 35898 

 3 US ARMY RSRCH OFFICE 

 J PRATER 

 D STEPP 

 D KISEROW 

 PO BOX 12211 

 RSRCH TRIANGLE PARK NC 

 27709-2211 

ABERDEEN PROVING GROUND

 26 DIR USARL 

 RDRL WM 

 J SMITH 

 S KARNA 

 J MCCAULEY 

 P PLOSTINS 

 RDRL WML 

 M ZOLTOSKI 

 J NEWILL 

 RDRL WML H 

 L MAGNESS 

 B SCHUSTER 

 RDRL WMM 

 R DOWDING 

 J ZABINSKI 

 RDRL WMM A 

 M MAHER 

 RDRL WMM B 

 M VANLANDINGHAM 

 RDRL WMM D 

 E CHIN 

 K CHO 

 RDRL WMM E 

 M PEPI 

 RDRL WMM F 

 B BUTLER 

 W DE ROSSET 

 L KECSKES 

 F KELLOGG 

 E KLIER 

 B KLOTZ 

 H MAUPIN 

 RDRL WMM G 

 A RAWLETT 

 RDRL WMP 

 P BAKER 

 S SCHOENFELD 
24

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