Dynamic Devitrification of Bulk Metallic Glasses (BMGs) 

and Composites of BMG With Tungsten 

by Laszlo J. Kecskes, Robert H. Woodman, and Samuel F. Trevino 

ARL-TR-3568 August 2005 

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Army Research Laboratory 

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ARL-TR-3568 August 2005 

Dynamic Devitrification of Bulk Metallic Glasses (BMGs) 

and Composites of BMG With Tungsten 

Laszlo J. Kecskes and Samuel F. Trevino 

Weapons and Materials Research Directorate, ARL 

Robert H. Woodman

Dynamic Science Inc. 

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Dynamic Devitrification of Bulk Metallic Glasses (BMGs) and Composites of 

BMG With Tungsten 

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Laszlo J. Kecskes, Robert H. Woodman,* and Samuel F. Trevino 

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14. ABSTRACT 

The penetration behavior of tungsten-bulk metallic glass (BMG) matrix composites is expected to be strongly influenced by the 

deformation behavior of the BMG matrix. It has been hypothesized that when the BMC matrix, initially in its viscous, deeply 

undercooled state, is subjected to compressive loads under the rapid time scales during ballistic impact, it may become a liquid 

without devitrification. We have carried out a series of in-situ x-ray diffraction experiments at the Advanced Photon Source 

(APS) and the National Synchrotron Light Source (NSLS) on BMG samples while heating them. At the same time, we carried 

out differential thermal analysis experiments and analyzed the results using the Kissinger method to estimate the critical heating 

rates necessary to bypass devitrification. The data collected and results show that the heating rates available at either APS or 

NSLS were insufficient to verify the hypothesis. 

15. SUBJECT TERMS

bulk metallic glasses, athermal devitrification, heating rate, liquid 

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Laszlo Kecskes 

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iii

Contents 

List of Figures iv

List of Tables iv

1. Objective 1

2. Approach 3

2.1 Materials..........................................................................................................................4 

2.2 In-situ X-ray Diffraction .................................................................................................4

2.3 Estimate of Critical Heating Rate....................................................................................5 

3. Results 5

3.1 In-situ X-ray Diffraction .................................................................................................5

3.2 Critical Heating Rate.......................................................................................................9 

4. Conclusions 11

5. References 12

Distribution List 13 
iv

List of Figures 

Figure 1. Residual, glass-only BMG penetrator in RHA target. Entry point is to the left.............1 

Figure 2. Plot of limit velocity vs. density for various alloys.........................................................2 

Figure 3. Debye-Scherrer photograph of Vitreloy 105 at room temperature. ................................6 

Figure 4. Debye-Scherrer photograph of Vitreloy 105 at 500 °C...................................................6 

Figure 5. False-color image of XRD patterns from Vitreloy 105 taken at 6.39 °C/min.................7 

Figure 6. Plots of integrated intensity for Q = 21.3 nm–1 for Vitreloy 105 (also known 

as Alloy 20) for all heating rates. The arrows indicate the onset temperature, halfway 

point, and completion temperature for the transformation at each heating rate. .......................8 

Figure 7. Plot of halfway point vs. heating rate for Vitreloy 105. The equation is from a 

linear regression of the three points...........................................................................................8 

Figure 8. False-color image of XRD patterns taken from Hf 105 at 1.67 °C/min..........................9 

Figure 9. Typical DTA trace from Hf52.5Ti5Cu17.9Ni14.6Al10...........................................................9 

Figure 10. Kissinger plot for Hf 105 for To = 788K. ....................................................................10 

Figure 11. Kissinger plot for Hf 105, excluding the data point for β = 40 K/min........................11 

List of Tables 

Table 1. BMG test results. ..............................................................................................................4 

Table 2. Test results. .....................................................................................................................10 
1

1. Objective 

The objective of this investigation is to demonstrate that bulk metallic glasses (BMG) can be 

melted without undergoing devitrification. This would establish a basis for testing whether or 

not BMG-matrix penetrators undergo matrix melting during penetration. 

Microscopic examination of a rod of bulk metallic glass fired into a semi-infinite, rolledhomogeneous-armor (RHA) target yields evidence that the glass melts during penetration 

(figure 1). Residue from the rod on the penetrator wall exhibited cracks normally associated 

with solidification from a melt (known as shrinkage cracks). This, along with similar evidence 

from residual composite penetrators, led to the hypothesis that molten matrix material is ejected 

from tungsten-BMG composite penetrators during penetration. 

Figure 1. Residual, glass-only BMG penetrator in RHA target. Entry point is to the left. 

If the matrix does melt during penetration, interpretation of the limit-velocity tests used to 

evaluate the effectiveness of penetrators will change. The limit velocity of BMG-tungsten 

composites has been interpreted as being due to a combination of the characteristic erosion 

mechanisms observed in two other materials—depleted uranium (DU) and tungsten heavy alloy 

(WHA). 

All other factors being equal, a more dense penetrator will exhibit a lower limit velocity, i.e., its 

penetration performance will be superior to a less dense material. WHA, which can be prepared 

in a range of densities from 16 to 19 g/cm3, exhibits this trend (figure 2). However, while DU 

alloys follow a similar trend, they also exhibit limit velocities measurably below those of WHAs 
2

Figure 2. Plot of limit velocity vs. density for various alloys. 

of comparable density. Furthermore, while DU alloys are less dense than pure tungsten, they 

exhibit superior penetration performance. 

It has been established that the penetration performance of DU relative to WHA is due to a 

difference in the erosion-and-discard mechanism for material at the penetrator tip (1). In 

tungsten and WHA, plastic deformation results in a broadening of the penetrator nose, which 

leads to a wider penetration tunnel than the initial diameter of the rod. In contrast, localized 

deformation of DU leads to sharpening of the nose, which leads to an overall greater depth of 

penetration. 

Tungsten-BMG composites were developed because metallic glasses deform and fracture by a 

localized mechanism similar to that seen in DU. Accordingly, the penetration performance of 

tungsten-BMG composites, which is intermediate between that of WHA and DU, has been 

interpreted as being a mix of plastic deformation and shear localization. 

If, in fact, molten metal is ejected from a tungsten-BMG composite during penetration, the limit 

velocities of such composites would need to be appreciated in light of such a third mechanism. 

The composite performance would be expected to reflect a mixture of the effect of ejection of 

molten matrix and plastic deformation of the tungsten. The nature of the limit-velocity-vs.-

density relationship for material which melts during penetration has not yet been studied. 

Much of the kinetic energy dissipated during penetration results in heating of both penetrator and 

target. What is unknown is whether or not the temperature rises high enough to exceed the glasstransition temperature (~500 °C) or liquidus temperature (~1000 °C) of a BMG. If the glassPenetrator Density (g/cc)

14 15 16 17 18 19 20

Limit Velocity (m/s)

1200

1300

1400

1500

1600

Tungsten Heavy Alloys

Uranium Alloy

Penetrator Density (g/cm3) 
3

transition temperature is exceeded, and the glass does not devitrify, the pressures experienced 

during penetration might be sufficient to cause the glass to behave like molten material. If the 

liquidus is exceeded, regardless of devitrification the matrix will be molten. 

Ballistic test facilities are not yet equipped to monitor temperature and microstructural changes 

in either penetrator or target (it would also be a challenge to adapt existing technology to do so in 

situ). Furthermore, because BMGs are a recent development, there are not yet physical models 

that might be used to estimate localized temperatures during penetration. 

To demonstrate that melting during penetration is possible, we undertook to monitor the 

structural changes in BMGs while heating them as rapidly as possible with available equipment. 

2. Approach 

In order to show that BMGs can be melted without devitrifying, we collected x-ray diffraction 

patterns from samples while heating them. The diffraction pattern of the amorphous structure of 

the glass differs noticeably from that of the crystalline devitrified material. If a sample were 

melted without devitrifying, it would retain the characteristic pattern of glasses and liquids 

throughout heating. If, on the other hand, the glass devitrified during heating, crystalline patterns 

would appear during the scan. In order to collect diffraction data of sufficient resolution, we 

found it necessary to use x-rays generated at synchrotron sources—the Advanced Photon Source 

(APS) at Argonne National Laboratory, and the National Synchrotron Light Source (NSLS) at 

Brookhaven National Laboratory. 

For the same reasons that cooling a melt to a glass without crystallization requires rapid cooling, 

melting a glass without devitrification requires rapid heating. Making glasses requires a 

minimum cooling rate—the critical cooling rate—to be achieved (2). Melting without 

devitrification requires that a critical heating rate be achieved. In order to estimate the critical 

heating rate, we conducted differential thermal analysis (DTA) of BMG samples and analyzed 

the results using the Kissinger method (3–6). Application of the Kissinger method to the 

devitrification kinetics of glasses has been analyzed in detail by Henderson (7). 

The Kissinger method relates the variation of DTA peak temperatures with heating rate to the 

activation energy of the physical process associated with the peak. A similar analysis can be 

used to calculate the heating rate which would be required to shift the peak temperature above a 

specific value. If the liquidus temperature is selected as the specific value, then the calculated 

heating rate is an estimate of the critical heating rate. 
4

2.1 Materials 

Two different BMGs were used in this study. Table 1 lists their names, compositions, glasstransition temperature (Tg), liquidus temperature (TL), and density. Vitreloy 105 is one of many 

zirconium-based BMG-forming alloys developed at the California Institute of Technology in the 

1990s (8). This class of alloys, known as Vitreloys, included some of the first BMGs to be made 

in sizes larger than 10 mm. Hf 105 is similar in composition to Vitreloy 105, with the zirconium 

replaced fully by hafnium, and was developed under the U.S. Army Research Laboratory’s 

Materials Center of Excellence program with Johns Hopkins University (9). Hf 105 represents 

an attempt to improve the ballistic performance of BMG-tungsten composites by raising the 

density of the BMG. Substitution of Hf for Zr in this formula increases the alloy density, but has 

deleterious effects on the glass-forming ability of the alloy. 

Table 1. BMG test results. 

Name Composition 

Tg

(°C) 

TL

(°C) 

Density 

(g/cm3

) 

Vitreloy 105 Zr52.5Ti5Cu17.9Ni14.6Al10 400 862 6.7 

Hf 105 Hf52.5Ti5Cu17.9Ni14.6Al10 467 1000 11.1 

2.2 In-situ X-ray Diffraction 

Tests at the APS were conducted at experimental station 6-ID-D (10). This instrument, 

administered by the Midwestern Universities Collaborative Access Team, delivers and detects 

x-rays with energies of 49.5–132.3 keV. This is 6–16 times higher than the 8.04 keV x-rays 

generated by typical laboratory x-ray generators. Consequently, the x-rays can fully penetrate 

samples which are 2–3 mm thick. Accordingly, the diffraction geometry for the experiments was 

in transmission, similar to electron diffraction in a transmission electron microscope. 

Diffraction patterns were collected using a charge-coupled device (CCD) camera detector (11). 

The camera was exposed to the scattered x-rays from the samples for 5-s spans at regular 

intervals during heating. A sample of suction-cast Vitreloy 105 was heated in an electric furnace 

in the incident x-ray beam at 6 °C/min from 350 to 500 °C. A total of 176 5-s exposures of the 

CCD camera were recorded during heating. Raw images from the CCD camera were analyzed 

using FIT2D, a program developed at the European Synchrotron Research Facility in Grenoble, 

France (12). 

Tests at the NSLS were conducted on beamline X-7B (13). The wavelength of the x-rays was 

0.92292 Å. A two-dimensional, position-sensitive detector was used to record the diffraction 

pattern. Samples of melt-spun Vitreloy 105 and Hf 105 were mounted in a tube of single-crystal 

sapphire heated by a high-resistance coil. A thermocouple inserted in the tube was used for 

temperature measurement. Diffraction patterns were recorded from samples of Vitreloy 105 

heated at 1.2, 2.4, and 6.4 °C/min, and from samples of Hf 105 heated at 1.67, 4.44, and 

11.92 o

C/min. 
5

2.3 Estimate of Critical Heating Rate 

Differential thermal analysis was performed using a Netzsch Instruments Simultaneous Thermal 

Analyzer model 409C, using graphite crucibles in an argon atmosphere. Samples of suction-cast 

Hf 105 were heated at four heating rates (5, 10, 20, and 40 K/min). 

Calculation of the critical heating rate involves rearranging the Kissinger-method equation: 

[ ( [ ] )]

[ ] R

E

d T T

d T T = − −

−

(1/ )

ln /

0

2 β 0 , (1) 

where β is the heating rate, Τ is the peak temperature, E is the activation energy, and R is the 

gas-law constant. T0 is a constant temperature determined from a fit of the DTA data to the 

Vogel-Tammann-Fulcher equation (14), following the procedure described by Henderson (7). 

It is clear from equation 1 that a plot of ( [ ] ) 2

0 ln β / T − T vs. [ ] 0

1

T − T will have a slope of 

R − E . That is: 

[ ] [ ] B T T M

T T ⎟ +

⎠

⎞ ⎜

⎝

⎛ − =⎟

⎟

⎠

⎞ ⎜

⎜

⎝

⎛

− 0

2

0

ln β 1 , (2) 

where M is the slope and B is the intercept of the plot. Substituting the liquidus temperature of 

the alloy, TL, for T, β becomes the critical heating rate, βcrit. In other words, βcrit can be 

determined directly from the plot: 

( ) ( ) ⎥

⎦

⎤ ⎢

⎣

⎡

+ − = − B

T T

M T T

L

crit L

0

2

0 β exp . (3) 

3. Results 

3.1 In-situ X-ray Diffraction 

The first and last of the 176 diffraction patterns recorded at APS are presented in figures 3 and 4. 

It is quite clear from figure 4 that the sample devitrified during heating. The diffuse ring visible 

in figure 3, characteristic of scattering from liquids and glasses, has been replaced in figure 4 by 

the distinct diffraction lines of a polycrystalline material. It is evident from this that 6 °C/min is 

lower than the critical heating rate. 
6

Figure 3. Debye-Scherrer photograph of Vitreloy 105 at room 

temperature. 

Figure 4. Debye-Scherrer photograph of Vitreloy 105 at 500 °C. 

Figure 5 is a false-color image of the diffraction patterns from Vitreloy 105 across the 

temperature range 25–600 °C at a heating rate of 6.39 °C/min. Color represents scattering 

intensity as a function of Q (4πsin(θ)/λ, where 2θ is the scattering angle and λ the wavelength) 

and temperature. Figure 5 is a top-down view of the series of diffraction patterns as the 
7

Figure 5. False-color image of XRD patterns from Vitreloy 105 

taken at 6.39 °C/min. 

temperature rises. The broad streak evident from room temperature up to just over 400 °C is the 

diffuse scattering from the glass structure. It is analogous to the diffuse ring in figure 3. The 

more numerous, sharp streaks at higher temperatures are the diffraction peaks from the 

devitrified material. It is clear from figure 5 that the glass devitrifies between 400 and 500 °C. 

The diffuse band between 20 and 30 nm–1 is the broad scattering peak from a glass structure, 

while the bright streaks at higher temperatures are the diffraction peaks from the crystalline 

structure. 

Figure 6 plots the integrated intensity vs. temperature for the peak at Q = 21.3 nm–1. Calculated 

averages of raw data in a finite Q interval centered at a given Q value are shown as data points 

(this is the same as the integrated intensity of a peak centered on a given value of 2θ). The data 

for each heating rate are scaled to obtain comparable maximum intensities. It is clear from the 

plot that the effect of increasing the heating rate is to expand the range of temperature over 

which the devitrification reaction occurs. Plots for the peaks at 34.7 nm–1 and 40.9 nm–1 have a 

similar appearance. 

Figure 7 is a plot of the temperature, T1/2, at which the integrated intensity of the 21.3 nm-1 peak 

is at 50% of its maximum value (a measure of when devitrification is 50% complete) vs. the 

heating rate for the scan. Linear regression of the three points yields an equation which can be 

used to estimate the critical heating rate required to shift T1/2 above the liquidus value. 

Figure 8 is the false-color pattern from Hf 105 over a broader temperature range, and at a heating 

rate of 1.67 °C/min. It is clear from the figure that the devitrification of Hf 105 involves more 

than one phase transformation, because the streaks representing the crystalline pattern are 

different over different temperature ranges. 

600

500

400

300

200

100

Temperature (C)

10 20 30 40 50

Q (nm-1)

10

9

8

7

6

5

4

3

x10 3
8

Figure 6. Plots of integrated intensity for Q = 21.3 nm–1 for Vitreloy 105 (also 

known as Alloy 20) for all heating rates. The arrows indicate the 

onset temperature, halfway point, and completion temperature for 

the transformation at each heating rate. 

Figure 7. Plot of halfway point vs. heating rate for Vitreloy 105. The 

equation is from a linear regression of the three points. 

0

10000

20000

30000

40000

50000

300 350 400 450 500 550 600

dT/dt = 1.2 C/min

dT/dt = 2.4 C/min

dT/dt =6.4C/min

I

Temp C

390 C

425 C

454 C

492 C

466 C 540 C

Alloy #20 Q = 21.3 nm -1

420

430

440

450

460

470

480

490

500

1234567

T

1/2

 = 417+ 12.0 (dT/ dt)

T1/2

dT/dt
9

Figure 8. False-color image of XRD patterns taken from Hf 105 at 

1.67 °C/min. 

3.2 Critical Heating Rate 

Figure 9 is a typical DTA trace used in the Kissinger-method determination of the critical 

heating rate. The sharp peaks correlate to exothermic events as the sample is heated. Figure 9 

shows the devitrification of Hf 105 at 10 K/min. The temperature at which the peak of the first 

exotherm occurs is 559 °C (832 K). This is the peak used for the Kissinger analysis, i.e., the 

temperature at which this peak occurs is T in equations 1 and 2. 

Figure 9. Typical DTA trace from Hf52.5Ti5Cu17.9Ni14.6Al10.

800

600

400

200

Temperature (C)

10 20 30 40 50

Q (nm-1)

12

10

8

6

4

2

x10 3
10

Table 2 shows β, Τ, [ ] 0

1

T −T , and ln( /[ ] )

2 β T −T0 for all four tests (5, 10, 20, and 40 K/min). 

Using the data taken at 5 K/min, T0 (from equations 1–3) was determined to be 515 °C (788 K). 

Figure 10 is the Kissinger plot. Note that the data points do not fall on a straight line. Figure 11 

is a Kissinger plot that excludes the data for β = 40 K/min. This plot is linear. Using all four 

data points, βcrit was determined to be 32 K/s, or 1914 K/min. Using the three points with a 

linear fit, βcrit was 50 K/s, or 3000 K/min. 

Table 2. Test results. 

β

(K/s) 

T – TO

(K) 

[ ] 0

1

T T–

(K-1) 

[ ] )

2

0 ln( / β T –T

1/12 822 0.029455 –9.53468 

1/6 832 0.022753 –9.35786 

1/3 846 0.017197 –9.22466 

2/3 876 0.011306 –9.37034 

T0 = 788 K

y = -10.687x - 9.1563

R2

 = 0.4256

-9.6

-9.55

-9.5

-9.45

-9.4

-9.35

-9.3

-9.25

-9.2

0 0.005 0.01 0.015 0.02 0.025 0.03 0.035

1/(T-T0)

ln(β/[T-T0]

2

)

Figure 10. Kissinger plot for Hf 105 for To = 788K. 
11

T0 = 788 K

y = -25.328x - 8.7864

R2

 = 0.9993

-9.6

-9.55

-9.5

-9.45

-9.4

-9.35

-9.3

-9.25

-9.2

0 0.005 0.01 0.015 0.02 0.025 0.03 0.035

1/(T-T0)

ln(β/[T-T0]

2

)

Figure 11. Kissinger plot for Hf 105, excluding the data point for β = 40 K/min. 

4. Conclusions 

Heating rates of up to 12 °C/min are insufficient to achieve melting of typical BMGs without 

devitrification. All samples from which in-situ diffraction data were collected devitrified at 

temperatures below their liquidus. Furthermore, the results of the Kissinger-method analysis 

of the critical heating rate indicate that considerably higher heating rates (32–50 K/s, or 

1900–3000 K/min) are necessary to demonstrate that such melting is possible. 

The implications for the ballistic behavior of tungsten-BMG composites center around the 

possibility that heating rates during penetration approach the critical heating rate. Given the 

rates involved, it seems highly unlikely that the matrix can melt without devitrification. 

However, it is also clear that an unequivocal experimental test of the possibility awaits further 

development in experimental technology.
12

5. References 

1. Magness, L. S. High Strain Rate Deformation Behaviors of Kinetic Energy Penetrator 

Materials During Ballistic Impact. Mechanics of Materials 1994, 17, 147–154. 

2. Johnson, W. L. Bulk Glass-Forming Metallic Alloys: Science and Technology. MRS 

Bulletin 1999, 24, 42–56. 

3. Kissinger, H. E. Reaction Kinetics in Differential Thermal Analysis. Anal. Chem. 1957, 

29, 1702–1708. 

4. Wendlandt, W. W. Thermal Analysis; 3rd ed.; John Wiley & Sons: New York, NY, 1986, 

229. 

5. Cunningham, A. D.; Wilburn, F. W. Theory. In Differential Thermal Analysis; 

R. C. MacKenzie, Ed., Academic Press: New York, NY, 1970, 61. 

6. Pope, M. I.; Judd, M. D. Differential Thermal Analysis: A Guide to the Technique and its 

Applications; Heyden & Son, Ltd.: Bellmawr, NJ, 1977, 186. 

7. Henderson, D. W. Thermal Analysis of Non-Isothermal Crystallization Kinetics in GlassForming Liquids. J. Non-Cryst. Sol. 1979, 30, 301–315. 

8. Lin, X. H.; Ph.D. Thesis. California Institute of Technology, 1997. 

9. Gu, X.; Xing, L. Q.; Hufnagel, T. C. J. Non-Cryst. Sol. 2002, 311, 77–82. 

10. https://beam.aps.anl.gov/pls/apsweb/bd_display_pkg.display_beamline?i_beamline_id=6-

ID-D 

11. http://www.marresearch.com/ 

12. http://www.esrf.fr/computing/scientific/FIT2D/ 

13. http://www.nsls.bnl.gov/beamlines/beamline.asp?blid=X7B 

14. Scherer, G. W. Editorial Comments on a Paper by Gordon S. Fulcher. J. Am. Ceram. Soc.

1992, 75, 1060–1062. 
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 AMSTA ASF 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR QAC T C 

 J PAGE 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR M 

 D DEMELLA 

 PICATINNY ARSENAL NJ 

 07806-5000 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

15

 3 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR FSA 

 A WARNASH 

 B MACHAK 

 M CHIEFA 

 PICATINNY ARSENAL NJ 

 07806-5000 

 2 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR FSP G 

 M SCHIKSNIS 

 D CARLUCCI 

 PICATINNY ARSENAL NJ 

 07806-5000 

 2 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR CCH C 

 H CHANIN 

 S CHICO 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR QAC T 

 D RIGOGLIOSO 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 US ARMY ARDEC 

 INTELLIGENCE SPECIALIST 

 AMSTA AR WEL F 

 M GUERRIERE 

 PICATINNY ARSENAL NJ 

 07806-5000 

 9 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR CCH B 

 P DONADIA 

 F DONLON 

 P VALENTI 

 C KNUTSON 

 G EUSTICE 

 K HENRY 

 J MCNABOC 

 R SAYER 

 F CHANG 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 PM ARMS 

 SFAE GCSS ARMS 

 BLDG 171 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 COMMANDER 

 US ARMY ARDEC 

 AMSTA AR WEA 

 J BRESCIA 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 PM MAS 

 SFAE AMO MAS 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 PM MAS 

 SFAE AMO MAS 

 CHIEF ENGINEER 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 PM MAS 

 SFAE AMO MAS PS 

 PICATINNY ARSENAL NJ 

 07806-5000 

 2 PM MAS 

 SFAE AMO MAS LC 

 PICATINNY ARSENAL NJ 

 07806-5000 

 1 COMMANDER 

 US ARMY TACOM 

 PM COMBAT SYSTEMS 

 SFAE GCS CS 

 6501 ELEVEN MILE RD 

 WARREN MI 48397-5000 

 1 COMMANDER 

 US ARMY TACOM 

 AMSTA SF 

 WARREN MI 48397-5000 

 1 DIRECTOR 

 AIR FORCE RESEARCH LAB 

 MLLMD 

 D MIRACLE 

 2230 TENTH ST 

 WRIGHT PATTERSON AFB OH 

 45433-7817 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

16

 1 OFC OF NAVAL RESEARCH 

 J CHRISTODOULOU 

 ONR CODE 332 

 800 N QUINCY ST 

 ARLINGTON VA 22217-5600 

 1 COMMANDER 

 US ARMY TACOM 

 PM SURVIVABLE SYSTEMS 

 SFAE GCSS W GSI H 

 M RYZYI 

 6501 ELEVEN MILE RD 

 WARREN MI 48397-5000 

 1 COMMANDER 

 US ARMY TACOM 

 CHIEF ABRAMS TESTING 

 SFAE GCSS W AB QT 

 T KRASKIEWICZ 

 6501 ELEVEN MILE RD 

 WARREN MI 48397-5000 

 1 COMMANDER 

 WATERVLIET ARSENAL 

 SMCWV QAE Q 

 B VANINA 

 BLDG 44 

 WATERVLIET NY 12189-4050 

 

 2 HQ IOC TANK 

 AMMUNITION TEAM 

 AMSIO SMT 

 R CRAWFORD 

 W HARRIS 

 ROCK ISLAND IL 61299-6000 

 2 COMMANDER 

 US ARMY AMCOM 

 AVIATION APPLIED TECH DIR 

 J SCHUCK 

 FORT EUSTIS VA 23604-5577 

 1 NSWC 

 DAHLGREN DIV CODE G06 

 DAHLGREN VA 22448 

 2 US ARMY CORPS OF ENGR 

 CERD C 

 T LIU 

 CEW ET 

 T TAN 

 20 MASSACHUSETTS AVE NW 

 WASHINGTON DC 20314 

 1 US ARMY COLD REGIONS 

 RSCH & ENGRNG LAB 

 P DUTTA 

 72 LYME RD 

 HANOVER NH 03755 

 13 COMMANDER 

 US ARMY TACOM 

 AMSTA TR R 

 R MCCLELLAND 

 D THOMAS 

 J BENNETT 

 D HANSEN 

 AMSTA JSK 

 S GOODMAN 

 J FLORENCE 

 D TEMPLETON 

 A SCHUMACHER 

 AMSTA TR D 

 D OSTBERG 

 L HINOJOSA 

 B RAJU 

 AMSTA CS SF 

 H HUTCHINSON 

 F SCHWARZ 

 WARREN MI 48397-5000 

 14 BENET LABS 

 AMSTA AR CCB 

 R FISCELLA 

 M SOJA 

 E KATHE 

 M SCAVULO 

 G SPENCER 

 P WHEELER 

 S KRUPSKI 

 J VASILAKIS 

 G FRIAR 

 R HASENBEIN 

 AMSTA CCB R 

 S SOPOK 

 E HYLAND 

 D CRAYON 

 R DILLON 

 WATERVLIET NY 12189-4050 

 1 USA SBCCOM PM SOLDIER SPT 

 AMSSB PM RSS A 

 J CONNORS 

 KANSAS ST 

 NATICK MA 01760-5057 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

17

 1 NSWC 

 TECH LIBRARY CODE B60 

 17320 DAHLGREN RD 

 DAHLGREN VA 22448 

 2 USA SBCCOM 

 MATERIAL SCIENCE TEAM 

 AMSSB RSS 

 J HERBERT 

 M SENNETT 

 KANSAS ST 

 NATICK MA 01760-5057 

 2 OFC OF NAVAL RESEARCH 

 D SIEGEL CODE 351 

 J KELLY 

 800 N QUINCY ST 

 ARLINGTON VA 22217-5660 

 1 NSWC 

 CRANE DIVISION 

 M JOHNSON CODE 20H4 

 LOUISVILLE KY 40214-5245 

 2 NSWC 

 U SORATHIA 

 C WILLIAMS CODE 6551 

 9500 MACARTHUR BLVD 

 WEST BETHESDA MD 20817 

 2 COMMANDER 

 NSWC 

 CARDEROCK DIVISION 

 R PETERSON CODE 2020 

 M CRITCHFIELD CODE 1730 

 BETHESDA MD 20084 

 8 DIRECTOR 

 US ARMY NGIC 

 D LEITER MS 404 

 M HOLTUS MS 301 

 M WOLFE MS 307 

 S MINGLEDORF MS 504 

 J GASTON MS 301 

 W GSTATTENBAUER MS 304 

 R WARNER MS 305 

 J CRIDER MS 306 

 2055 BOULDERS RD 

 CHARLOTTESVILLE VA 

 22911-8318 

 1 NAVAL SEA SYSTEMS CMD 

 D LIESE 

 1333 ISAAC HULL AVE SE 1100 

 WASHINGTON DC 20376-1100 

 7 US ARMY SBCCOM 

 SOLDIER SYSTEMS CENTER 

 BALLISTICS TEAM 

 J WARD 

 W ZUKAS 

 P CUNNIFF 

 J SONG 

 MARINE CORPS TEAM 

 J MACKIEWICZ 

 AMSSB RCP SS 

 W NYKVIST 

 S BEAUDOIN 

 KANSAS ST 

 NATICK MA 01760-5019 

 7 US ARMY RESEARCH OFC 

 A CROWSON 

 H EVERITT 

 J PRATER 

 G ANDERSON 

 D STEPP 

 D KISEROW 

 J CHANG 

 PO BOX 12211 

 RESEARCH TRIANGLE PARK NC 

 27709-2211 

 1 AFRL MLBC 

 2941 P ST RM 136 

 WRIGHT PATTERSON AFB OH 

 45433-7750 

 1 DIRECTOR 

 LOS ALAMOS NATL LAB 

 F L ADDESSIO T 3 MS 5000 

 PO BOX 1633 

 LOS ALAMOS NM 87545 

 8 NSWC 

 J FRANCIS CODE G30 

 D WILSON CODE G32 

 R D COOPER CODE G32 

 J FRAYSSE CODE G33 

 E ROWE CODE G33 

 T DURAN CODE G33 

 L DE SIMONE CODE G33 

 R HUBBARD CODE G33 

 DAHLGREN VA 22448 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

18

 1 NSWC 

 CARDEROCK DIVISION 

 R CRANE CODE 6553 

 9500 MACARTHUR BLVD 

 WEST BETHESDA MD 20817-5700 

 1 AFRL MLSS 

 R THOMSON 

 2179 12TH ST RM 122 

 WRIGHT PATTERSON AFB OH 

 45433-7718 

 2 AFRL 

 F ABRAMS 

 J BROWN 

 BLDG 653 

 2977 P ST STE 6 

 WRIGHT PATTERSON AFB OH 

 45433-7739 

 5 DIRECTOR 

 LLNL 

 R CHRISTENSEN 

 S DETERESA 

 F MAGNESS 

 M FINGER MS 313 

 M MURPHY L 282 

 PO BOX 808 

 LIVERMORE CA 94550 

 1 AFRL MLS OL 

 L COULTER 

 5851 F AVE 

 BLDG 849 RM AD1A 

 HILL AFB UT 84056-5713 

 1 OSD 

 JOINT CCD TEST FORCE 

 OSD JCCD 

 R WILLIAMS 

 3909 HALLS FERRY RD 

 VICKSBURG MS 29180-6199 

 3 DARPA 

 M VANFOSSEN 

 S WAX 

 L CHRISTODOULOU 

 3701 N FAIRFAX DR 

 ARLINGTON VA 22203-1714 

 1 OAK RIDGE NATL LAB 

 R M DAVIS 

 PO BOX 2008 

 OAK RIDGE TN 37831-6195 

 1 OAK RIDGE NATL LAB 

 C EBERLE MS 8048 

 PO BOX 2008 

 OAK RIDGE TN 37831 

 3 DIRECTOR 

 SANDIA NATL LABS 

 APPLIED MECHS DEPT 

 MS 9042 

 J HANDROCK 

 Y R KAN 

 J LAUFFER 

 PO BOX 969 

 LIVERMORE CA 94551-0969 

 1 OAK RIDGE NATL LAB 

 C D WARREN MS 8039 

 PO BOX 2008 

 OAK RIDGE TN 37831 

 4 NIST 

 M VANLANDINGHAM MS 8621 

 J CHIN MS 8621 

 J MARTIN MS 8621 

 D DUTHINH MS 8611 

 100 BUREAU DR 

 GAITHERSBURG MD 20899 

 1 HYDROGEOLOGIC INC 

 SERDP ESTCP SPT OFC 

 S WALSH 

 1155 HERNDON PKWY STE 900 

 HERNDON VA 20170 

 3 NASA LANGLEY RESEARCH CTR 

 AMSRD ARL VT 

 W ELBER MS 266 

 F BARTLETT JR MS 266 

 G FARLEY MS 266 

 HAMPTON VA 23681-0001 

 1 FHWA 

 E MUNLEY 

 6300 GEORGETOWN PIKE 

 MCLEAN VA 22101 

 1 USDOT FEDERAL RAILROAD 

 M FATEH RDV 31 

 WASHINGTON DC 20590 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

19

 3 CYTEC FIBERITE 

 R DUNNE 

 D KOHLI 

 R MAYHEW 

 1300 REVOLUTION ST 

 HAVRE DE GRACE MD 21078 

 1 DIRECTOR 

 NGIC 

 IANG TMT 

 2055 BOULDERS RD 

 CHARLOTTESVILLE VA 

 22911-8318 

 2 3TEX CORP 

 A BOGDANOVICH 

 J SINGLETARY 

 109 MACKENAN DR 

 CARY NC 27511 

 1 DIRECTOR 

 DEFENSE INTLLGNC AGNCY 

 TA 5 

 K CRELLING 

 WASHINGTON DC 20310 

 1 COMPOSITE MATERIALS INC 

 D SHORTT 

 19105 63 AVE NE 

 PO BOX 25 

 ARLINGTON WA 98223 

 1 JPS GLASS 

 L CARTER 

 PO BOX 260 

 SLATER RD 

 SLATER SC 29683 

 1 COMPOSITE MATERIALS INC 

 R HOLLAND 

 11 JEWEL CT 

 ORINDA CA 94563 

 1 COMPOSITE MATERIALS INC 

 C RILEY 

 14530 S ANSON AVE 

 SANTA FE SPRINGS CA 90670 

 1 SIMULA 

 R HUYETT 

 10016 S 51ST ST 

 PHOENIX AZ 85044 

 2 PROTECTION MATERIALS INC 

 M MILLER 

 F CRILLEY 

 14000 NW 58 CT 

 MIAMI LAKES FL 33014 

 2 FOSTER MILLER 

 M ROYLANCE 

 W ZUKAS 

 195 BEAR HILL RD 

 WALTHAM MA 02354-1196 

 1 ROM DEVELOPMENT CORP 

 R O MEARA 

 136 SWINEBURNE ROW 

 BRICK MARKET PLACE 

 NEWPORT RI 02840 

 2 TEXTRON SYSTEMS 

 M TREASURE 

 T FOLTZ 

 1449 MIDDLESEX ST 

 LOWELL MA 01851 

 1 O GARA HESS & EISENHARDT 

 M GILLESPIE 

 9113 LESAINT DR 

 FAIRFIELD OH 45014 

 1 MILLIKEN RESEARCH CORP 

 M MACLEOD 

 PO BOX 1926 

 SPARTANBURG SC 29303 

 1 CONNEAUGHT INDUSTRIES INC 

 J SANTOS 

 PO BOX 1425 

 COVENTRY RI 02816 

 1 ARMTEC DEFENSE PRODUCTS 

 S DYER 

 85 901 AVE 53 

 PO BOX 848 

 COACHELLA CA 92236 

 3 PACIFIC NORTHWEST LAB 

 M SMITH 

 G VAN ARSDALE 

 R SHIPPELL 

 PO BOX 999 

 RICHLAND WA 99352 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

20

 1 ALLIANT TECHSYSTEMS INC 

 4700 NATHAN LN N 

 PLYMOUTH MN 55442-2512 

 1 APPLIED COMPOSITES 

 W GRISCH 

 333 NORTH SIXTH ST 

 ST CHARLES IL 60174 

 1 CUSTOM ANALYTICAL 

 ENG SYS INC 

 A ALEXANDER 

 13000 TENSOR LANE NE 

 FLINTSTONE MD 21530 

 1 AAI CORP 

 DR N B MCNELLIS 

 PO BOX 126 

 HUNT VALLEY MD 21030-0126 

 1 OFC DEPUTY UNDER SEC DEFNS 

 J THOMPSON 

 1745 JEFFERSON DAVIS HWY 

 CRYSTAL SQ 4 STE 501 

 ARLINGTON VA 22202 

 3 ALLIANT TECHSYSTEMS INC 

 J CONDON 

 E LYNAM 

 J GERHARD 

 WV01 16 STATE RT 956 

 PO BOX 210 

 ROCKET CENTER WV 

 26726-0210 

 1 PROJECTILE TECHNOLOGY INC 

 515 GILES ST 

 HAVRE DE GRACE MD 21078 

 1 PRATT & WHITNEY 

 C WATSON 

 400 MAIN ST MS 114 37 

 EAST HARTFORD CT 06108 

 5 NORTHROP GRUMMAN 

 B IRWIN 

 K EVANS 

 D EWART 

 A SHREKENHAMER 

 J MCGLYNN 

 BLDG 160 DEPT 3700 

 1100 W HOLLYVALE ST 

 AZUSA CA 91701 

 1 BRIGS COMPANY 

 J BACKOFEN 

 2668 PETERBOROUGH ST 

 HERNDON VA 22071-2443 

 1 ZERNOW TECHNICAL SERVICES 

 L ZERNOW 

 425 W BONITA AVE STE 208 

 SAN DIMAS CA 91773 

 2 GENERAL DYNAMICS OTS 

 FLINCHBAUGH DIV 

 K LINDE 

 T LYNCH 

 PO BOX 127 

 RED LION PA 17356 

 1 GKN WESTLAND AEROSPACE 

 D OLDS 

 450 MURDOCK AVE 

 MERIDEN CT 06450-8324 

 5 SIKORSKY AIRCRAFT 

 G JACARUSO 

 T CARSTENSAN 

 B KAY 

 S GARBO MS S330A 

 J ADELMANN 

 6900 MAIN ST 

 PO BOX 9729 

 STRATFORD CT 06497-9729 

 1 AEROSPACE CORP 

 G HAWKINS M4 945 

 2350 E EL SEGUNDO BLVD 

 EL SEGUNDO CA 90245 

 2 CYTEC FIBERITE 

 M LIN 

 W WEB 

 1440 N KRAEMER BLVD 

 ANAHEIM CA 92806 

 2 UDLP 

 G THOMAS 

 M MACLEAN 

 PO BOX 58123 

 SANTA CLARA CA 95052 

 2 UDLP 

 R BRYNSVOLD 

 P JANKE MS 170 

 4800 E RIVER RD 

 MINNEAPOLIS MN 55421-1498 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

21

 1 LOCKHEED MARTIN 

 SKUNK WORKS 

 D FORTNEY 

 1011 LOCKHEED WAY 

 PALMDALE CA 93599-2502 

 1 NORTHRUP GRUMMAN CORP 

 ELECTRONIC SENSORS 

 & SYSTEMS DIV 

 E SCHOCH MS V 16 

 1745A W NURSERY RD 

 LINTHICUM MD 21090 

 1 GDLS DIVISION 

 D BARTLE 

 PO BOX 1901 

 WARREN MI 48090 

 2 GDLS 

 D REES 

 M PASIK 

 PO BOX 2074 

 WARREN MI 48090-2074 

 1 GDLS 

 MUSKEGON OPER 

 M SOIMAR 

 76 GETTY ST 

 MUSKEGON MI 49442 

 1 GENERAL DYNAMICS 

 AMPHIBIOUS SYS 

 SURVIVABILITY LEAD 

 G WALKER 

 991 ANNAPOLIS WAY 

 WOODBRIDGE VA 22191 

 6 INST FOR ADVANCED 

 TECH 

 H FAIR 

 I MCNAB 

 P SULLIVAN 

 S BLESS 

 W REINECKE 

 C PERSAD 

 3925 W BRAKER LN STE 400 

 AUSTIN TX 78759-5316 

 1 ARROW TECH ASSOC 

 1233 SHELBURNE RD STE D8 

 SOUTH BURLINGTON VT 

 05403-7700 

 1 R EICHELBERGER 

 CONSULTANT 

 409 W CATHERINE ST 

 BEL AIR MD 21014-3613 

 1 SAIC 

 G CHRYSSOMALLIS 

 8500 NORMANDALE LAKE BLVD 

 SUITE 1610 

 BLOOMINGTON MN 55437-3828 

 1 UCLA MANE DEPT ENGR IV 

 H T HAHN 

 LOS ANGELES CA 90024-1597 

 1 UMASS LOWELL 

 PLASTICS DEPT 

 N SCHOTT 

 1 UNIVERSITY AVE 

 LOWELL MA 01854 

 1 IIT RESEARCH CTR 

 D ROSE 

 201 MILL ST 

 ROME NY 13440-6916 

 1 GA TECH RESEARCH INST 

 GA INST OF TCHNLGY 

 P FRIEDERICH 

 ATLANTA GA 30392 

 1 MICHIGAN ST UNIV 

 MSM DEPT 

 R AVERILL 

 3515 EB 

 EAST LANSING MI 48824-1226 

 1 PENN STATE UNIV 

 R S ENGEL 

 245 HAMMOND BLDG 

 UNIVERSITY PARK PA 16801 

 1 PENN STATE UNIV 

 C BAKIS 

 212 EARTH ENGR 

 SCIENCES BLDG 

 UNIVERSITY PARK PA 16802 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

22

 1 PURDUE UNIV 

 SCHOOL OF AERO & ASTRO 

 C T SUN 

 W LAFAYETTE IN 47907-1282 

 1 UNIV OF MAINE 

 ADV STR & COMP LAB 

 R LOPEZ ANIDO 

 5793 AEWC BLDG 

 ORONO ME 04469-5793 

 1 JOHNS HOPKINS UNIV 

 APPLIED PHYSICS LAB 

 P WIENHOLD 

 11100 JOHNS HOPKINS RD 

 LAUREL MD 20723-6099 

 1 UNIV OF DAYTON 

 J M WHITNEY 

 COLLEGE PARK AVE 

 DAYTON OH 45469-0240 

 5 UNIV OF DELAWARE 

 CTR FOR COMPOSITE MTRLS 

 J GILLESPIE 

 M SANTARE 

 S YARLAGADDA 

 S ADVANI 

 D HEIDER 

 201 SPENCER LAB 

 NEWARK DE 19716 

 1 DEPT OF MTRLS 

 SCIENCE & ENGRG 

 UNIV OF ILLINOIS 

 AT URBANA CHAMPAIGN 

 J ECONOMY 

 1304 W GREEN ST 115B 

 URBANA IL 61801 

 1 MISSISSIPPI STATE UNIV 

 DEPT OF AEROSPACE ENGRG 

 A J VIZZINI 

 MISSISSIPPI STATE MS 39762 

 1 DREXEL UNIV 

 A S D WANG 

 3141 CHESTNUT ST 

 PHILADELPHIA PA 19104 

 3 UNIV OF TEXAS AT AUSTIN 

 CTR FOR ELECTROMECHANICS 

 J PRICE 

 A WALLS 

 J KITZMILLER 

 10100 BURNET RD 

 AUSTIN TX 78758-4497 

 1 SOUTHWEST RESEARCH INST 

 ENGR & MATL SCIENCES DIV 

 J RIEGEL 

 6220 CULEBRA RD 

 PO DRAWER 28510 

 SAN ANTONIO TX 78228-0510 

 3 DIRECTOR 

 US ARMY RESEARCH LAB 

 AMSRD ARL WM MB 

 A FRYDMAN 

 2800 POWDER MILL RD 

 ADELPHI MD 20783-1197 

ABERDEEN PROVING GROUND

 1 US ARMY ATC 

 CSTE DTC AT AC I 

 W C FRAZER 

 400 COLLERAN RD 

 APG MD 21005-5059 

 112 DIR USARL 

 AMSRD ARL CI 

 AMSRD ARL O AP EG 

 M ADAMSON 

 AMSRD ARL SL BA 

 AMSRD ARL SL BB 

 D BELY 

 AMSRD ARL WM 

 J SMITH 

 AMSRD ARL WM B 

 CHIEF 

 T KOGLER 

 AMSRD ARL WM BA 

 D LYON 

 AMSRD ARL WM BC 

 J NEWILL 

 P PLOSTINS 

 AMSRD ARL WM BD 

 P CONROY 

 B FORCH 

 M LEADORE 

 C LEVERITT 

 R LIEB 
NO. OF NO. OF 

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23

 R PESCE-RODRIGUEZ 

 B RICE 

 A ZIELINSKI 

 AMSRD ARL WM BF 

 S WILKERSON 

 AMSRD ARL WM M 

 J MCCAULEY 

 S MCKNIGHT 

 AMSRD ARL WM MA 

 CHIEF 

 L GHIORSE 

 E WETZEL 

 AMSRD ARL WM MB 

 J BENDER 

 T BOGETTI 

 J BROWN 

 L BURTON 

 R CARTER 

 K CHO 

 W DE ROSSET 

 G DEWING 

 R DOWDING 

 W DRYSDALE 

 R EMERSON 

 D GRAY 

 D HOPKINS 

 R KASTE 

 L KECSKES (25 CPS) 

 M MINNICINO 

 B POWERS 

 D SNOHA 

 J SOUTH 

 M STAKER 

 J SWAB 

 J TZENG 

 AMSRD ARL WM MC 

 CHIEF 

 R BOSSOLI 

 E CHIN 

 S CORNELISON 

 D GRANVILLE 

 B HART 

 J LASALVIA 

 J MONTGOMERY 

 F PIERCE 

 E RIGAS 

 W SPURGEON 

 AMSRD ARL WM MD 

 B CHEESEMAN 

 P DEHMER 

 R DOOLEY 

 G GAZONAS 

 S GHIORSE 

 M KLUSEWITZ 

 W ROY 

 J SANDS 

 D SPAGNUOLO 

 S WALSH 

 S WOLF 

 AMSRD ARL WM RP 

 J BORNSTEIN 

 C SHOEMAKER 

 AMSRD ARL WM T 

 B BURNS 

 AMSRD ARL WM TA 

 W BRUCHEY 

 M BURKINS 

 W GILLICH 

 B GOOCH 

 T HAVEL 

 C HOPPEL 

 E HORWATH 

 J RUNYEON 

 M ZOLTOSKI 

 AMSRD ARL WM TB 

 P BAKER 

 AMSRD ARL WM TC 

 R COATES 

 AMSRD ARL WM TD 

 D DANDEKAR 

 M RAFTENBERG 

 S SCHOENFELD 

 T WEERASOORIYA 

 AMSRD ARL WM TE 

 CHIEF 

 J POWELL 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION

24

 1 LTD 

 R MARTIN 

 MERL 

 TAMWORTH RD 

 HERTFORD SG13 7DG 

 UK 

 1 CIVIL AVIATION 

 ADMINSTRATION 

 T GOTTESMAN 

 PO BOX 8 

 BEN GURION INTRNL AIRPORT 

 LOD 70150 

 ISRAEL 

 1 AEROSPATIALE 

 S ANDRE 

 A BTE CC RTE MD132 

 316 ROUTE DE BAYONNE 

 TOULOUSE 31060 

 FRANCE 

 1 DRA FORT HALSTEAD 

 P N JONES 

 SEVEN OAKS KENT TN 147BP 

 UK 

 1 SWISS FEDERAL ARMAMENTS 

 WKS 

 W LANZ 

 ALLMENDSTRASSE 86 

 3602 THUN 

 SWITZERLAND 

 1 DYNAMEC RESEARCH LAB 

 AKE PERSSON 

 BOX 201 

 SE 151 23 SODERTALJE 

 SWEDEN 

 1 ISRAEL INST OF TECHLGY 

 S BODNER 

 FACULTY OF MECHANICAL 

 ENGR 

 HAIFA 3200 

 ISRAEL 

 1 DSTO 

 WEAPONS SYSTEMS DIVISION 

 N BURMAN RLLWS 

 SALISBURY 

 SOUTH AUSTRALIA 5108 

 AUSTRALIA 

 1 DEF RES ESTABLISHMENT 

 VALCARTIER 

 A DUPUIS 

 2459 BLVD PIE XI NORTH 

 VALCARTIER QUEBEC 

 CANADA 

 PO BOX 8800 COURCELETTE 

 GOA IRO QUEBEC 

 CANADA 

 1 ECOLE POLYTECH 

 J MANSON 

 DMX LTC 

 CH 1015 LAUSANNE 

 SWITZERLAND 

 1 TNO DEFENSE RESEARCH 

 R IJSSELSTEIN 

 ACCOUNT DIRECTOR 

 R&D ARMEE 

 PO BOX 6006 

 2600 JA DELFT 

 THE NETHERLANDS 

 2 FOA NATL DEFENSE RESEARCH 

 ESTAB 

 DIR DEPT OF WEAPONS & 

 PROTECTION 

 B JANZON 

 R HOLMLIN 

 S 172 90 STOCKHOLM 

 SWEDEN 

 2 DEFENSE TECH & PROC 

 AGENCY GROUND 

 I CREWTHER 

 GENERAL HERZOG HAUS 

 3602 THUN 

 SWITZERLAND 

 1 MINISTRY OF DEFENCE 

 RAFAEL 

 ARMAMENT DEVELOPMENT 

 AUTH 

 M MAYSELESS 

 PO BOX 2250 

 HAIFA 31021 

 ISRAEL 

 1 B HIRSCH 

 TACHKEMONY ST 6 

 NETAMUA 42611 

 ISRAEL 
NO. OF 

COPIES ORGANIZATION 

25

 1 DEUTSCHE AEROSPACE AG 

 DYNAMICS SYSTEMS 

 M HELD 

 PO BOX 1340 

 D 86523 SCHROBENHAUSEN 

 GERMANY 
26

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