Army Research Laboratory 

Aberdeen Proving Ground, MD 210055069 

ARL-TR-2365 November 2000 

Functional Nanostructures for Induction 

Heating: A Review of Literature and 

Recommendations for Research 

Bruce K. Fink 

Weapons and Materials Research Directorate, ARL 

Shridhar Yarlagadda, John Q. Xiao, Gary H. Laverty, and 

John W. Gillespie, Jr. 

University of Delaware 

Approved for public release; distribution is unlimited. 
Abstract 

This report presents the concept for a multidisciplinary research program aimed at 

establishing the science base for the design and synthesis of magnetic nanoparticles for 

hysteresis heating, with potential applications ranging from novel composites processing 

techniques to alternative cancer treatments. Magnetic materials are used in a wide range 

of applications and designed for maximum efficiency or minimized hysteresis loss. The 

uniqueness of this project is that, while considerable work has been aimed at reducing 

hysteresis losses, the converse effect (i.e., increasing hysteresis losses and therefore heat 

generation) has not been fully studied. Hysteresis-based heating has several advantages 

over conventional heating techniques, including the fact that it is a very rapid and 

noncontact process. In addition, the Curie temperature of magnetic materials can also be 

used as a means of “smart” thermal control. Exploratory basic research through ongoing 

programs at the U.S. Army Research Laboratory (ARL) has established the feasibility of 

Curie temperature control and demonstrated the effects of particle size, frequency, and 

stoichiometry on hysteresis losses. The following scientific barriers are addressed in this 

report: magnetization dynamics in high-frequency magnetic fields, the effects of 

magnetic phase transition on hysteresis heating, and the dimensional dependence of Curie 

temperature in nanoparticles. If carried out, the research program outlined in this report 

would establish the science base for the design and synthesis of nanoparticles for 

hysteresis heating applications. 

ii 
. 

‘Table of Contents 

Paae 

List of Figures .-....... . . . . ..~........*~......*.......*.....**....*...~.**..*..............*.....~.*..... .*.......... V 

1. Introduction . . . . . . *. . . . . . . e .. . . ..~..*.~*.*~..~...~.~.............~..*......~.....~..* . . . ..*...***..*...**..*...** . . . . . . 1 

2. Scientific Barriers in Particle Design . . . . . . . . . ..*...................*...........**...........*... m *...... 6 

2.1 

2.2 

2.3 

2.4 

Issues 6 ..................................................... 

.............................................................. 

Particle Synthesis ...................................................................... 6 .......................... 

Dynamics of Magnetic Domain Wall Motion.. ................................................... 9 

Ferromagnetic to Paramagnetic Phase Transition and Superparamagnetic 

Relaxation ........................................................................................................... 14 

3. Potential Applications . . . . . . . . . . . . . .,,,..,..*....... .,.. . . . . . . . . . . . . . .- . ..*... .-..... . . . . . ..-........... 17 

3.1 Polymer Processing ............................................................................................. 

3.2 Selective Cell Death.. .......................................................................................... 

3.2.1 Experimental Cell Bioassays.. ....................................................................... 

3.2.2 Heating Tests ................................................................................................. 

3.2.3 Cell Death Assays.. ........................................................................................ 

17 

20 

21 

22 

22 

4. summary ....................................................................................... 23 

........................... 

4.1 Particle Design 23 . . . . . . . . . . . . . . . e .. . . , . . . ..*.....*...~..............* ~......~..*.,..~.......*....*~......**....*..~.~ 

4.2 Polymer Processing . . . . ..**.~..f........**.**~*.. .*...*.....**.......***.... . . . . ...*............*...........***. 23 

4.3 Selective Cell Death . . . . . e .. . . . . . . . . . . . . . . . . . . . . . . . . . ..~.~~~...~.......... . . . . . . ..*..*........***..~f . . . ...**... 24 

5. References 25 .. . . . . . . . . . . . . . . . . . . . . . . . . ..*.***...*.........*.*..... . . . ..*.*......**.......***..... . . . ..**.*..*.........***... 

Distribution List -........... . . . . . ...*...*.*.........**.*.*.. . . . ..f.*.................*....~......*.*...........~*.. 35 

Report Documentation Page *..* .. . . . . . . . . . . . . . . . . . . . . ..~~.....*.*...............**..........*****..........*.* 55 

. . . 

111 
bIl%NTIONALLY ~FT~LANK. 

iv 
List of Figures 

Fiwe 

1. Multidisciplinary Research Effort in Hysteresis Heating of Magnetic Nanoparticles 

for Biological and Polymer Processing Applications. _.+ . . . . ..f._____~f.f..._____......__.._____f..f 

2. Schematic of Domain Wall Motion Due to External Field... _..,......~.-._,....*.,..-f....*..-.. 

3. Schematic Representation of the Random Anisotropy Model _f________....f._._ ___f..fff _ ___.. 

4. Coercivity vs. Grain Sized for Various Soft Magnetic Materials . . . . . . . ..___........___._____. 

5. Self-Regulating Temperature Profile for Ferromagnetic Polymer Susceptor _..-f..__ 

V 

m 

2 

11 

13 

14 

18 
&l-ENTIONALLYLEFT BLANK. 

vi 
1. Introduction 

The goal of this report is to outline the research requirements to establish the science base for 

the design and synthesis of nanoparticles for hysteresis heating, with potential applications 

ranging from novel polymer processing techniques to alternative cancer treatments. This report 

outlines a multidisciplinary research approach encompassing physics, material science, and 

biology research areas. The proposed research focuses on maximizing hysteresis losses in 

magnetic particle systems, while research to date has focused on minimizing hysteresis losses. 

As shown in Figure 1, a multidisciplinary research approach would enable advances in the basic 

science of hysteresis heating in magnetic nanoparticles and subsequent optimization of these 

nanoparticles for potential use in biological and polymer processing applications. 

Interest in the study of nanostructured materials has increased rapidly during the past several 

years, stimulated by recent advances in materials synthesis and characterization techniques. 

These materials are of great scientific interest in developing a better understanding of magnetic 

phenomena. Their unique structure offers a fertile ground to study size, surface/interface, and 

intra- and interparticle interaction effects [l-3]. These materials are being used in a wide range 

of applications, including magnetic tapes, ferrofluids, catalysts; medical diagnostics, drug 

delivery systems, and pigments in paints and ceramics [ 1, 2, 4-61. As never before, magnetic 

materials are the key to the future of the storage industry [7-131. 

Research on fine magnetic particles started in the late 1940s [ 14, 15 ]and peaked in the 

1950s. One of the milestones of that development was the emergence of domain theory [ 161, 

which led to the conceit of single domain particles [17] and magnetic anisotropy contributions, 

giving rise to permanent magnet behavior [ 18 3 and superparamagnetism [ 191. Stimulated by the 

potential application of fme magnetic particles in magnetic recording media [20,21], most recent 

studies have concentrated on magnetization and coercivity [ 1, 21, magnetic reversal mechanism 

[22-251, and superparamagnetic relaxation [26, 271. The dynamics of fine magnetic particles, 

including phenomena such as domain wall resonance and spin resonance, have rarely been 

1 
Fabrication and Characterization 

of Magnetic Nanonartlcles 

Particle Svnthesis & 

Characterization 

*Particle fabrication 

l Particle, grain size 

*Curie temperature 

*Hysteresis loss 

v 1 

Modeling 

aDomain wall Induction Heating 

dynamics aHysteresis vs heat 

l Fundamental t ? 

generation 

understanding l Curie temperature 

*Optimum frequency of heat generation 

dynamics *Power requirements 

I 

c 

Optimized Magnetic 

Nanoparticle Svstem 

l Heat Generation 

aCurie Temperature 

*Optimum Frequency 

*Minimum Power 

Tc - 30-80 “C Tc- 100400 “C 

I 

Selective Cell Death 

l Particle Injection in Cells 

aNecrosis &d Apoptosis in 

I 

- Single Cell 

- Cell Culture 

Figure 1. Multidisciplinary Research Effort in Hysteresis Heating of Magnetic 

Nanoparticles for Biological and Polymer Processing Applications. 

1. 

2 
studied, except in the superparamagnetic region. These phenomena are directly related to the 

conversion of energy absorbed from external magnetic fields to heat. 

In most applications of magnetic nanoparticles, heat generation is not desirable. However, 

induction-based hysteresis heating has several features that can be exploited for efficient and 

economical heating. Two applications proposed as part of this effort use hysteresis heating of 

particles. The first involves induction heating for processing of advanced polymers; the second 

is targeted at the use of magnetic nanoparticles for selective heating and destruction of cells. The 

proposed effort addresses the scientific barriers to magnetic nanoparticle design for controlled 

heating. 

Exploratory basic research at the U.S. Army Research Laboratory (ARL) at Aberdeen 

Proving Ground (APG) and the University of Delaware has established the feasibility of 

hysteresis heating for polymer processing [28-311, and an invention has been disclosed on this 

technology [32]. Existing processing techniques for polymers have time and cost limitations that 

can be overcome by hysteresis heating. In the repair of high-performance polymer composites 

where the thermal requirements are stringent, self-controlled heating based on the Curie 

temperature of the material is ideal. In addition, by using nanoparticles as additive tillers, one 

can easily adapt existing processing techniques for hysteresis-heating-based processing of 

polymers. New research is required to quantify the heat-generation capabilities of a variety of 

magnetic nanoparticle systems and the use of Curie temperature as a built-in “smart” thermal 

control system. 

Hyperthermia in the treatment of cancer is well established in terms of the required 

temperatures and dwell cycles for cellular thermal shock, thermotolerance buildup from heat 

shock proteins, apoptosis, and rapid therrnoablation [33-391. The most clinically effective and 

desirable means of imposing thermal energy for hyperthertnia is to inject a susceptor material 

directly into the target cells. This allows localization of thermal energy into the target cells 

alone. In order to be acceptable for hyperthennia treatment for humans, the susceptor material 

must be injectable into the cellular structure, must remain localized to the target cells for 

3 
subsequent treatment, and must not cause clinical complications. In order to be effective, the 

susceptor material, or ferrofluid, must be energetically able to remain in suspension, must be 

capable of rapid heating to the correct “process” temperature to minimize electromagnetic 

radiation exposure time for the patient, must have a Curie temperature that provides for precise 

control of temperature, and must have sufficient hysteretic properties such that the volumetric 

percentage of loading of particles is minimized. Most research to date has focused on the former 

“acceptibility” issues and not on the latter “effectiveness” issues. The proposed work would 

focus on the latter enabling issues for cancer treatment. 

Magnetic materials have been considered for a number of therapeutic applications, including 

contrast imaging [40], magnetic guidance of drugs or radionucleides to selected target sites [41], 

and hyperthermic destruction of cells using inductive heating methods [421c4]. The latter 

application represents an important advance in cancer therapy and is the focus of this report. 

Two major obstacles to the implementation of such an approach can be imagined: (1) selective 

targeting of particles to specific cells and (2) optimization of particle and heating parameters to 

destroy those cells with minimal collateral damage. In addition, there are numerous other 

considerations, such as toxicity, metabolic clearance of particles, intracellular vs. extracellular 

efficacy, and precise control of heat production in the target area, vis-a-vis blood flow patterns, 

tissue density, etc. While many of these issues have been considered [42, 44463, there has been 

little systematic investigation of nanoparticle properties in a reproducible bioassay. Thus, one 

objective of any new research thrust should be to develop such bioassays, based on nanoparticleinduced hyperthermic cell death. 

Used in a wide range of applications, magnetic materials are designed for maximum 

efficiency or minimized power loss. One mechanism of power loss in these materials is 

magnetic hysteresis loss, which results in heating of the material. While considerable work has 

been aimed at reducing hysteresis losses, the converse effect-i.e., increasing hysteresis losses 

and therefore heat generation-has not been fully studied. 
-. 

c 

r 

Hysteresis-based heating has several inherent advantages over other heating techniquesl Energy input is noncontact. 

l Heating can be very rapid (-50 “C/s). 

l Heating can be self-controlling based on the Curie temperature of the material. 

In order to fully exploit the potential of hysteresis heating, work is necessary to understand 

the relationships between hysteresis heating and material parameters, such as composition and 

particle size. Nanoscale particles allow us the flexibility of (1) using size-property relationships 

to maximize hysteresis losses, (2) minimizing eddy current losses such that Curie temperature 

can be for smart temperature control, and (3) maximizing particle-polymer interphase to 

optimize thermal and mechanical properties. 

The following outlines a three-step research effort on the design and application of hysteresis 

heating of magnetic nanoparticles. 

(1) Establish the science base to understand the hysteresis behavior of magnetic 

nanoparticles as a function of particle parameters, magnetic field, and frequency. 

(2) Develop materials by design based on the physics of magnetic particles. With the 

science base established, given the heating requirements for specific applications, one 

can easily determine the specific material parameters to be used; this will involve 

fabricating of nanoparticles of a variety of compositions and particle sizes, 

characterizing of the magnetic and heating properties, and theoretical modeling to 

optimize particle preparation. 

(3) Identify and demonstrate two potentially high-gain applications using the following 

nanoparticles: 

5 
. Curie temperature control-based polymer processing, and 

l selective cell death-necrosis and apoptpsis. 

2. Scientific Barriers in Particle Design 

2.1 Issues. For these objectives to be met, several basic issues in the physics of magnetic 

particles must be addressed. 

. Development of reliable and controllable methods to synthesize nanoparticles. 

l Development of an understanding of the magnetization dynamics in high-frequency 

magnetic fields, with the ultimate goal being to maximize the energy loss, which is 

minimized in traditional applications. These high-frequency behaviors, which have 

rarely been studied, are of great scientific interest, relating magnetic tunneling, domain 

wall damping, and domain wall resonance phenomena. 

l Investigation of the effects of magnetic phase transition on hysteresis heating (energy 

loss); the magnetic transition of a nanoparticle encompasses ferromagnetic, 

superparamagnetic, and pammagnetic phases. 

. Application-based identification of particle composition, size, microstructure, induction 

power, and frequency for maximum heat generation or power loss at a specified Curie 

temperature. The Curie temperature is chosen based on the applications; 100-400 “C for 

polymer processing and 3&80 “C for cell death studies. 

2.2 Particle Synthesis. There are numerous techniques for preparing fine particles [1, 21. 

These include electrodeposition [47 1, reducing transition metal ions by NaB& or KB& [48--S 13, 

sol-gel processes [%!I, spark erosion [53-551, aerosol pyrolysis [56], gas evaporation [20, 571, 

sputtering [26, 581, gas and water atomization [59], reverse micelle techniques [60-631, and 

mechanical ball milling (MB) [64-66]. MB, unlike, many of the aforementioned methods, 

6 
produces its nanostructures not by cluster assembly but by the structure decomposition of coarsegrained structures as the result of severe plastic deformation in a cyclic process. This has 

become a popular method to make nanocrystalline materials because of its simplicity, the 

relatively low cost of the equipment needed, and the applicability of the method to essentially all 

classes of materials. Another major advantage is the potential for easily scaling up to tonnage 

quantities of materials for various applications. 

It is necessary to first distinguish between nanoparticles and nanograin/nanocrystalline 

particles. The former refers to particles of nanometer size that generally consist of a single grain, 

and the latter to particles consisting of many grains of nanometer size. The nanograin particle 

may not be nanometer in size. For brittle materials, such as oxides, nitrides, carbides, and rare 

earth-transition metal intermetallic compounds, MB can indeed produce nanoparticles [67], 

whereas for ductile materials, straight MB will produce only nanograin particles because of the 

excessive cold welding. The nanoparticles can, however, be fabricated either using various 

surfactants (hexane) [68-701 or milling the material in an oxygen or hydrogen atmosphere and 

deoxidizingdehydriding the final powders [59]. Both nanoparticles and nanograin particles are 

relevant to this research, as discussed in the following paragraphs. 

A detailed microscopic model of the development of a nanocrystalline structure by MB is 

still lacking, although there is some agreement on the phenomenological model, which comprises 

three stages [64,65]. 

(1) Deformation Stage-the deformation is localized in shear bands containing a high 

dislocation density. 

(2) Nanograin Forrnationdislocations annihilate and recombine to form nanograins with 

small-angle grain boundaries. Further milling extends this structure throughout the 

sample. 

7 
(3) Nanograin Randomization-the orientation of the grains becomes random, probably 

through grain boundaries by sliding or rotating. 

These deformation processes are important for fundamental studies of extreme mechanical 

deformation and for developing a nanostructured state of matter with particular physical and 

chemical properties. The mechanisms of dislocation vs. grain boundary deformation can be 

distinguished by studying the atomic-level lattice strain (E) and the stored enthalpy (AH) as a 

function of reciprocal grain size. At stage 1, both lattice strain and enthalpy depend weakly on 

grain size. A large jump in the values of E and AH signifies the transition into stages 2 and 3. 

Finally, both E and AH reach a maximum value before decreasing. The causes of such maxima 

are still under debate [66, 71-741. It is important to identify the microstructure in which optimal 

magnetic properties can be realized. 

Magnetic particles can be fabricated using a shake mill and a computer-controlled attrition 

mill. The latter has a variable rotor speed of up to 1,500 rpm, with a capacity up to 500 cm3. 

Particles can be made in vacuum, gas atmosphere, or solution. For alloys, small particles are 

made either through mechanical alloying (mixing powders) or milling down the alloys, which are 

made using arc melting or vacuum-induction furnaces. Magnetic oxide particles, which may be 

more friendly to biological cells, can also be made using powders, which are readily available. 

To achieve the nanoparticle size for ductile materials, two methods will be used. Materials can 

be ball-milled in an oxygen or hydrogen environment. The interstitial oxygen/hydrogen or 

oxides/hydrides tend to make materials brittle. The final nanoparticles will be treated in a high 

vacuum to remove/disassociate the oxygen or hydrogen. An alternative way to fabricate 

nanoparticles is to add surfactants, usually a hexane solution, during the ball milling. For 

example, extremely soft aluminum and magnesium powders can be milled to form small alloy 

particles in the presence of sodium-l, 2 bis (dedecyl carbonyl) ethane-1-sulfonate or lithium-l,2 

bis dodecyloxycarbonyl sulfasuccinate [68], and (Co-Fe)7&5B10 soft magnets can be milled 

down to about 100 nm in diameter in the presence of sodium-l,2 bis (dedecyl carbonyl) ethane1 -sulfonate or ammonium dihexadecyl dimethylacetate. 
Particle size and grain size can be characterized using x-ray, electron microscopy, and 

particle analyzers (GALAI CISl 00 and Brookhaven Instrument Bl-XDC). The GALAI CISlOO 

analyzer measures particles from 0.5 to 600 pm in size by measuring the rotating laser time of 

shadowing, with additional particle shape analysis using a rapid video microscope picture 

analyzer. The Brookhaven analyzer uses centrifugal analysis with an x-ray detector and is 

capable of measuring particles from 10 mn to 10 pm in size. The stored enthalpy will be 

measured using differential scanning calorimetry (DSC) by integrating the exothermal signals. 

The structure will be carefully characterized and optimized to produce maximum heat. Such 

optimization can be achieved through adjusting rotor speed and adding appropriate surfactank 

A common problem encountered with milling fine particIes is the potential for significant 

contamination from the milling media (balls and vial) or atmosphere. Such contamination can be 

significantly reduced using a low-energy mill [66], which can be achieved in our attrition mill by 

reducing the rotor speed. It has recently been shown [73] that the minimum nanocrystalline 

grain size for a number of elements milled in a low-energy mill is comparable to that from a 

high-energy mill [71, 74, 751. Surfactants may also be used to minimize contamination. For 

example, boric acid and borax were quite effective in reducing iron contamination [76]. Our 

attrition mill is also capable of fabricating materials in a vacuum environment, thus minimizing 

atmospheric contamination. 

2.3 Dynamics of Magnetic Domain Wall Motion. Many of the specific applications of 

magnetic materials depend on their behavior at high frequencies. When subjected to an 

alternating field, magnetic permeability shows dependence on several magnetization 

mechanisms. As the field frequency increases, magnetic moments are unable to follow the 

applied field because of “microeddy currents” generated by the ac field near the domain walls. 

Consequently, there is a lag between the applied field and the magnetization of the material, 

resulting in hysteresis-type behavior. The permeability becomes a complex number, and the 

imaginary part of the permeability corresponds to the energy dissipation. This energy dissipation 

appears in the form of heat and is commonly called hysteresis heating. In all nonheating 

9 
applications, hysteresis heating should be minimized; however, the proposed applications require 

the converse (maximum hysteresis heating and desired Curie temperature T,). 

The frequency spectrum for each magnetization mechanism is different, since each has a 

different time constant. In bulk materials, such as ferrites, the low-frequency (MHz) peak is 

associated with domain wall dynamics and the high-frequency peak, usually in the GHz range, 

with spin resonance. There are very few studies on the dynamics of magnetic particles, and the 

emphasis was exclusively on quantum tunneling behavior, which appear at sub-Kelvin 

temperature and low frequency (4 MHz) [77, 781. The study of particle dynamics will not only 

lead to a new understanding of their behavior in ac fields, but also significantly impact both 

heating and nonheating applications, as more materials based on particles are used. 

Consider a 180” domain wall, as shown in Figure 2; an external magnetic 

exerts a pressure on and bows the Bloch wall, displacing it a distance h(z) in 

These displacements approximately obey the equation [79, 801 

d2h d*h 

-- 

‘dz2 m dt2 

--+h =-2M,H(h), 

field H(x,z)eio’ 

the x-direction. 

(1) 

where all the coefficients are defined per unit area. The first term represents the wall energy, and 

y is the wall surface tension. The second term is the wall inertia, and m is the effective wall 

mass. The third term is the relaxation damping term opposing wall propagation, and the last 

term is associated with wall pinning due to defects, expressed as a restoring force. The equation 

resembles a harmonic oscillator and has no analytical solution. Many assumptions have been 

made in order to solve the equation-e-g., either rigid or flexible plane walls (no bowing) were 

used in the Polivanov model [31] and the Pry and Bean model [82], respectively. In the models 

where wall bowing is considered, a linear response approximation was always used [79] (either 

H is not a function of h or only a linear term is considered). 

10 
Most recently, in an attempt to explain results on the frequency response of iron-cobalt soft 

magnetic materials at high temperatures [X3], Chui reconsidered the problem [84]. Consider the 

situation shown in Figure 2; in addition to equation (I), the equation for H was also derived as 

follows: 

where 0 is electric conductivity. To avoid any simplifying assumptions, a numerical method was 

used to solve the equations. Similarly, core losses, which correspond to heat generation, can also 

be calculated by integrating jE = oE’. The electric field E can be calculated using VxE = 

l/c(dBldt) = M,/c(&@t). The first-order approximation, in the case shown in Figure 2, leads to 

VxE z 2E, and core loss will be proportional to the domain wall speed (ah/&)2. However, a 

detailed solution should be obtained by solving equations (1) and (2) self-consistently. 

x 

Figure 2. Schematic of Domain Wall Motion Due to External Field. 

With some modifications, the previous method can be applied to magnetic particles. 

Particularly, anisotropy and dipolar energy, which scale with particle size, have to be considered. 

11 
The interplay between exchange interaction, anisotropy, and dipolar interaction leads to the 

formation of edge domains. The formation of edge domains and magnetization reversal 

mechanisms have recently been studied theoretically with the Monte-Carlo simulation by Chui 

using 4 x 4 x 12 “block spins” in nanosize thin films [8S], particles, and nanowires [86]. The 

finite element block spin, in which all atomic spins are aligned, is chosen so that the detail of 

domain formation can still be clearly seen, and the computing power (time) is minimized. 

Consequently, a relatively large sample can be simulated. For example, the block spin of soft 

magnetic materials is chosen to be much larger than that in hard magnetic materials. 

It is crucial to relate the heat generation (core loss) to material parameters (exchange 

coupling constant [J], anisotropy constant [Kr], and microstructure, such as grain size and 

particle size). The wall energy y in equation (4) is related to (JIQ)‘“, and the restoring force will 

include the dipolar term. 

For nanoparticles where only a single domain exists, the coherent rotation is believed to be 

due to the reversal mechanism [23, 24, 871. However, recent theory has suggested that even in 

very small particles, edge domains exist [86]; in most experiments, domains always nucleate 

because of impurities, dislocations, and surface boundary effects. In MB samples, the impurities 

and dislocations are expected to be high, and magnetization reversal is almost certainly due to 

domain wall motion. The theoretical approach presented for the dynamics of magnetic domain 

wall motion is thus applicable to our study. 

For nanocrystalline particles, domain walls can easily nucleate and move rapidly because of a 

much smaller effective anisotropy IQ. Therefore, significant heat generation is expected from 

these nanocrystalline particles. The effective anisotropy and dipolar interaction can be 

calculated using a random anisotropy model that was originally developed by Cullan, Yu arid 

Cullen [88] and Alben, Becker, and Chui [89] for amorphous materials. The basic idea, sketched 

in Figure 3, starts f-ram an assembly of ferromagnetically coupled grains of size D with 

magnetocrystalline anisotropies of I& oriented at random. The effective anisotropy affecting the 

magnetization process results from an average over the N = (L&)3 grains with the volume 

12 
Figure 3. Schematic Representation of the Random Anisotropy Model. 

V = LeX3, where L,, = (IUK~)“~ is the ferromagnetic exchange length and A the exchange 

stiffness. For a finite number (N) of grams, there will always be a preferred direction determined 

by statistical fluctuations. Consequently, the resulting anisotropy density c K, > is determined 

by the mean fluctuation amplitude of the anisotropy energy of the N grains (i.e., 

<K, >Z l&l&). This random anisotropy model was applied to explain the behavior of 

nanocrystalline materials by Herzer [90, 911 using a dimensionality-like argument. The average 

magnetocrystalline anisotropy, < R, > , is predicted to scale with the structural correlation length 

D as < K;x K,(D/L& and coercive field and permeability is thus scaled with D6. 

Experimental data shows this correlation (Figure 4). The dipolar term (g), which scales with 

grain size as &(LJD)3, can also be included in simulations. 

The frequency spectrum of nanocrystalline particles and nanoparticles can be simulated as a 

function of external field, frequency, anisotropy constant, and particle and grain size. In 

particular, the peak in the complex component of permeability, which signifies domain wall 

resonance, can be investigated as a function of these parameters. The information on particle 

and grain size can be used to design the structure, and material composition can be selected 

based on exchange and anisotropy constants. The induction system parameters, such as field and 

frequency, will be optimized to maximize heating. The core loss and permeability spectrum of 

the designed material can be measured using a high-frequency hysteresis loop tracer and an 

impedance analyzer. 

13 
Figure 4. Coercivity vs. Grain Size D for Various Soft Magnetic Materials: Fe-Nb-Si-B 

(A), Fe-Cu-Nb-Si-B (m), Fe-Cu-V-Si-B (+), Fe-Zr-B (Q Fe-Co-Zr (v), 

FeNi-Alloys (A and II), and FeSi 6.5 weight-percent (0). 

2.4 Ferromagnetic to Paramagnetic Phase Transition and Superparamagnetic 

Relaxation. The second-order magnetic transition from the ferromagnetic to the paramagnetic 

phase is characterized by the T,, above which no energy will be absorbed from the external 

magnetic field and thus no heat will be generated. When nanoscale magnetic particles are 

embedded in an insulating matrix, negligible heat will be generated from eddy currents. 

Therefore, the T, can be used as a smart temperature controller, above which heat generation will 

automatically shut off. 

The T, can be varied by alloying different materials or using different particle sizes. The 

latter has not been studied, mainly due to superparamagnetic relaxation. For a single domain 

particle, when thermal energy is high enough to overcome the energy barrier that restricts the 

spins from switching direction, the magnetic moments within a particle can rotate rapidly in 

unison [92-941. This behavior resembles the paramagnetic phase, except that the particle carries 

14 
a giant moment (sum of individual atomic moments in the whole particle), hence the term 

“superparamagnetism.” The susceptibility (x) in a paramagnetic phase can be written as 

x (emu/v) = 

N&A )’ 

%(T-4 ’ 

(3) 

where N is the number of pararnagnetic moments of an effective atomic moment perpB, and ka 

is the Boltzrnann constant- In the case of a superparamagnet, N is the number of magnetic 

particles per unit volume and peg pa is the magnetization of the magnetic particles, which is 

many times higher than the atomic moment. Clearly, the slopes associated with two phases in 

the l/x vs. T curve will be different, and the T, can thus be determined. It should be pointed out 

that the particle size distribution may complicate the analysis. However, since the moments 

associated with the two phases are very different, the determination of T, is possible. As an 

independent check, T, can also be measured using DSC [95] and by performing specific-heat 

measurements. 

It is important to determine whether the superparamagnetism will affect induction heating, 

which is typically carried out in the k&-MHz frequency range. The simplest form of the 

superparamagnetic relaxation time (z) can be described by the Arrhenius relation [87] 

r = rOexp(KVlk, T), (4) 

where ro is the characterization time and KV is the total anisotropy energy (energy barrier) 

including magnetocrystalline, shape, and magnetoelastic anisotropies. In the case of iron and 

FesoNi50, large values of K, in excess of 10’ erg/cm3, have been observed [96-981. This 

enhancement of K in part accounts for the very large coercivities observed in magnetic particles 

[993, which can significantly increase the hysteresis loss and heat generation. The value of TO 

was estimated to be 10-l’ s from neutron diffraction data [ 1001 and lo-l3 s from Superconducting 

Quantum Interference Device (SQUID) magnetometer and Miissbauer spectroscopy [97]. 

15 
Therefore, considering a magnetic particle of 10 nm at T = 300 K, the relaxation rate (l/z) is 

much smaller than the frequency of interest (0.1 to 100 MHz). Therefore, these moment 

rotations have no impact on induction heating. f 

Although the dimensional dependence of T, in nanoparticles has not been studied, it has been 

found that finite-size scaling [ 1011 can be used to explain phase transition behavior in reduced 

dimension structures. This theory predicts that the shift in the transition temperature from that of 

the bulk should depend on a dimension of the system in the following manner: 

Tc w -T&4 I dd ( 1 -1 

T,W - 2 ’ (5) 

where d is the sample dimension, and do should be of the order of the characteristic microscope 

dimension of the system, such as the lattice parameter. The exponent h is predicted to be related 

to the correlation length exponent by h=l/v. 

This behavior has been widely observed in the T, of multilayer ferromagnetic systems [ 1021 

and spin freezing temperature (T,) in spin-glass systems [ 103, 1041. The spin freezing 

temperature in granular materials has also been found to follow the finite-size scaling rule [26]. 

The only study on T, of nanoparticles was done using ferrites [lOS], where the value of T, was 

found to increase with decreasing particle size. This observation was later argued to be due to 

the less-random cation distribution for large particles and not to fmite size effects [ 106, 1071. 

An alternative and more reliable way to control the T, is to use alloys. A wide selection of 

materials is available (e.g., FexCrlOO _ X [0 -L x < 70, 770 “C >T, > 0 “Cl, Ni,Crroo- X [0 < x < 8, 

370 “C >T, >O “Cl, and Ni,Culoo _ X [0 < x < 40, 370 “C >T, > 0 “Cl). These alloys also have 

excellent corrosion and oxidation resistance. The disadvantage is the low magnetization 

compared to pure magnetic elements, which may reduce the heat generation capability. A study 

of T, in magnetic nanoparticles should address the issues of dimensional dependence and alloy 

16 
composition and enable an investigation into the scaling relation in the zero dimension. To study 

the true TC, particles can be embedded in a polymer or ceramic matrix to eliminate inter-particle 

interactions. 

3. Potential Applications 

A number of fundamental issues in nanoparticle design--particle size, frequency, 

stoichiometry, and T,--are common to the two applications that will be explored in this research 

program. The science base for design and synthesis of nanoparticles for hysteresis heating that 

will be developed as part of the proposed effort will provide a starting point for identifying 

nanoparticle systems that can be used in the two proposed applications. 

3.1 Polymer Processing. Electromagnetic induction is a well-known and widely used 

heating technique for metals and alloys. More recently, significant research [108-l 161 has been 

undertaken to adapt induction-heating techniques to polymers for benefits such as reduced cost 

and processing times. Heat generation, in a material subjected to an alternating magnetic field, 

occurs due to joule-type losses [log, 112, 1151 (using metal mesh susceptors) or hysteresis 

[ 117-l 191 (using magnetic particles). Both techniques can result in very rapid localized heating, 

which is ideal for polymer processing. 

Existing polymer processing, bonding, and repair techniques require autoclaves, which have 

size restrictions and are quite costly. Rapid, noncontact, and localized heating will allow for 

accelerated cure of thermosetting polymers or the rapid interdiffusion of thermoplastic polymers 

by concentrating energy at the interphase of interest. The design and controlled multiaxis motion 

of the induction coil can also cure complex polymer composite parts. The advantages of 

induction-assisted processing include reduced cost and processing time per part, rapid 

manufacturing, and the potential for increased design complexity. 

Of the two heat-generation techniques, hysteresis heating is the focus of this report. A 

significant advantage to this technique over joule-heating techniques is using the T, of the 

17 
ferromagnetic material as a means of automatic or smart temperature control. By choosing 

materials such that T, is within the processing temperature window of the polymer, one can 

automatically control the process temperature. However, one must also ensure that hysteresis 

heating is the sole heat-generation mechanism (no joule losses), and this can be achieved by 

using well-dispersed particles in the polymer. An example of this concept is shown in Figure 5. 

The nickel/polysulphone susceptor shows very rapid rise to steady-state temperature (-350 “C) 

once the induction coil is activated and then maintains the temperature regardless of any increase 

in input power. Polysulphone is a commercially used thermoplastic with a manufacturerrecommended processing window between 300 and 360 “C, and nickel has a T, of 354 OC, 

resulting in an ideal combination0 

iTmax = 360 “C 

I I T I I I , I I I I , r I I I I I 

50 100 150 200 

Time (seconds) 

:Tmin = 300 Y 

- 1.0 

- 0.8 

- 0.6 ‘p 

g 

Ea 

- 0.4 5 

Figure 5. Self-Regulating Temperature Profile for Ferromagnetic Polymer Susceptor. 

The Two Horizontal Lines at 300 “C and 360 “C Represent the Lower and Upper 

Bounds on the Process, Respectively. 

18 
. 

19 

By choosing ferromagnetic particle systems with T, between 100 and 400 OC, it is possible to 

process any thermoset or thermoplastic with a built-in smart temperature control capability. In 

addition, by using the nanoparticles as additive fillers in the polymer, one can easily adapt 

existing processing techniques for hysteresis-heating-based processing of composites, with 

minimal loss in mechanical performance. 

The science base for designing and synthesizing nanoparticles for hysteresis heating can 

provide a starting point in identifying ferromagnetic nanoparticle systems that can be used for 

polymer processing. Thermal requirements or cure cycles for the processing of polymers should 

be used to determine the optimal nanopatticle system, particle parameters and induction power, 

and frequency requirements. Ideally, it is desired that the power input, frequency and particle 

loading be as low as possible for sufficient heating to completely process the polymer. 

Initial tests may focus on heat-transfer dynamics in nanoparticle/polymer systems. A 

calorimeter-type setup could be built into a hysteresis loop tracer to measure heat generation and 

correlated with ac hysteresis measurements of the particle system. Nanoparticles could be mixed 

with polymers for test samples, with particle size, particle composition, volume fraction, 

magnetic field, and frequency being the parameters. Particles could be mixed with polymers by 

either solvent casting techniques (e.g., dimethylacetamide and polysulphone) or milling particles 

with polymer powders and compression molding (e.g., milled nickel particles in polysulphone 

powder, molded at 350 “C). In both techniques, oxidation of nanoparticles could be minimized 

by reducing the exposure to air or using surface-treated particles. Effects of exposure to 

controlled environments (oxygen and air) on particle heating characteristics should also be 

quantified. Nanoparticle distribution in the polymer, could be examined and quantified using 

SEM and TEM and then used as input for heat transfer simulations. Key results guiding the 

design of nanoparticles include actual polymer temperature, as compared to particle Tc, 

automatic temperature control capability, and heat generationBased on a finite element model for heat-transfer simulations in particle/polymer systems, 

nanoparticle systems that meet the thermal requirements for polymer processing could be 
identified to ensure that particles are viable and optimized. Thin films could be fabricated using 

the polymer and nanoparticle system by solvent casting or compression molding and used in the 

polymer bonding and cure demonstrations. A new concept for curing polymers and composites 

using hybrid films consisting of different size particles could also be investigated. Typical 

polymer cure cycles involve multiple temperature steps and dwell times. For example, a typical 

350 “F (177 “C) thermoset (TS) may be cured by heating to 250 “F (121 “C), dwelling for 1 hr, 

and then heating to 350 “F (177 “C) and dwelling for 2 hr. The same steps can be duplicated 

using a two-material hybrid nanoparticle system and induction heating, with one material having 

T, near 250 “F (121 “C) and the other near 350 “F (177 “C) and different optimal frequencies 

(-700 kHz and -4-5 MHz) for maximum heating. 

3.2 Selective Cell Death. The biological component described in this report is designed to 

directly test the ability of intracellular nanoparticles to cause selective cell death. These 

experiments would examine how varying parameters such as particle size, composition, and 

density, as well as induction frequency and power level, can be used to optimize hyperthermic 

damage. Hyperthermia is generally thought to cause immediate cell damage and necrosis 

through protein denaturing and loss of membrane integrity. However, more recent work has also 

demonstrated effects of moderate (43-46 “C) hyperthermia on DNA damage and apoptosis in 

various cells, both directly [120-1231 and with lag periods requiring restoration of normal 

incubation temperatures [ 1241. Therefore, these experiments should examine both primary 

necrosis and apoptosis at varying times after hyperthermic treatment. Success in selective 

necrosis and apoptosis would allow the development of nanoparticle-based alternative treatments 

for cancer. 

The general approach is to microinject magnetic nanoparticle suspensions of varying 

composition into individual cells, subject these cells to inductive heating of varying degree and 

time, and assay for cell death. Initial experiments could be performed on uninjected cells 

subjected to passive heating in a DSC to determine the sensitivity and onset of cell death or 

necrosis and apoptosis to such variables as rate of temperature change, maximum temperature 

exposure, and length of exposure. Optimal values of temperature rates, maximum temperature, 

20 
and duration of exposure would dictate the choice of magnetic nanoparticles and parameters for 

induction-heating experiments. 

3.2.1 Experi~entul Cell Bioassays. Two types of cell systems are commonly used to study 

nanoparticle heating properties. The first is the amphibian (Xenopus) oocyte model, widely used 

in microinjection protocols for ribo-nucleic acid (RNA) expression studies or in-vitro’ 

fertilization studies [125-1271. To isolate individual oocytes, ovarian lobes are dissected from 

anesthetized frogs. A total of 10 to 50 stage V-VI oocytes are then removed and manually 

defolliculated by blunt dissection [125, 12X]. Each cell is placed in a well, formed from the 

mesh of a piece of Nitex filter placed in a Petri dish. The cells are immersed in a modified 

Barth’s solution (MBS). The oocytes can then be rapidly microinjected under a stereo 

microscope using a micromanipulator and an injection system (PicoPump, WPI, Inc.). 

Micropipettes are prepared from l-mm glass capillaries with internal fiber, pulled on a Kopf 

pipette puller, and beveled to a final tip diameter of 5-10 FM. Generally, injected volumes are 

10-50 nl (2-10% of cell volume). Injected cells are then transferred to individual wells of a 96 

well culture plate, containing MBS with 0.2% Trypan blue dye to screen for membrane integrity 

(dye exclusion assay). This model system allows for rapid screening of nanoparticle properties 

at the individual cell level. 

The second assay system consists of cell cultures in various configurations. Both continuous 

cell lines, including 3T3 fibroblasts and MDCK kidney epithelial cells, and primary cell cultures 

of rat liver would be assayed. Cells lines are maintained at 37 “C in appropriate growth media 

(DMEM, RPMI 1640) with fetal bovine serum and subcultured at intervals of 7-14 days. For 

experiments, cells are plated onto 35-mm collagen-coated plastic Petri dishes. Rat hepatocyte 

cultures are generated using a collagenase dissociation method [ 1291 and cultured on an artificial 

extracellular matrix (Matrigel, Becton Dickinson). Both the continuous and primary cell lines 

could be used in either subconfluent or confluent configurations to assess collateral damage at 

varying distances from the microinjected target cell. Single cells are microinjected as previously 

described, except using an .inverted, compound microscope with phase contrast optics, 

micropipets with smaller tip diameters of approximately 1 urn, and reduced injection volumes. 

21 
Following injection, the culture medium is replaced with physiological salt solution containing 

0.2% Trypan blue. Induction-heating and cell death assays would bc performed on the entire 

monolayer. Controls would include both oocytes and cultured cells injected with carrier solution 

alone, as well as nanoparticle-injected cells not subjected to the induction heating. The latter 

would provide information about the cytotoxicity of nanoparticles. 

3.2.2 Heating Tests. Individual microinjected oocytes or cultured monolayers could be 

subjected to heating protocols of varying intensity and duration. Initial tests would use a DSC 

for passive heating under controlled conditions, with known heating rate, maximum temperature, 

and duration of heating. These tests will help determine the ‘ideal heating conditions for cell 

death. Heating rates and maximum temperature would determine the composition, particle size, 

and T, of the magnetic nanoparticle system, as well as the power and frequency of the induction 

heating system. 

Individual cell and cell cultures would be microinjected with the selected nanoparticle system 

and inductively heated according to the heating conditions determined by DSC tests; cell death 

could then be assessed. It is expected that the induction-heating tests would duplicate the DSC 

test results and demonstrate the feasibility of this application. The fmal step would be to assess 

collateral damage and investigate means to mitigate it; this could be done by injecting selected 

cells with magnetic nanoparticles and assessing damage to surrounding cells after induction 

heating. 

3.2.3 Cell Death Assays. Immediately after the thermal challenge, cells are examined under 

light microscopy for Trypan blue uptake. Positive staining indicates loss of membrane integrity 

and necrosis. Negative cells are then transferred back to an incubator set at normal growth 

temperature (37 “C) and monitored for an additional, variable period of l-6 hr. At varying times 

during this period (l-6 hr post-treatment), some cells would also be assayed for apoptosis. The 

assay system is based on an in-situ fluorescence variation of the TUNEL (TdT-mediated dUTPX nick end labeling) method (In Situ Cell Death Detection Kit, Boehringer Mannheim). Briefly, 

this method allows direct fluorescence visualization of apoptotic cells, based on the predictable 

22 
DNA fragmentation that accompanies apoptosis and the use of the enzyme terminal 

deoxynucleotidyl transferase to attach fluorescent derivatives to free 3’-OH groups on the DNA 

strands. This approach would allow for rapid screening of apoptosis in individual microinjected 

oocytes, as well as target and collateral cell death in cultured monolayers. 

4, Summary 

The goal of this multidisciplinary research would be to establish the science base for the 

design and synthesis of nanoparticles for hysteresis heating, with potential applications ranging 

from novel polymer processing techniques to alternative cancer treatments. This research plan 

would focus on muximizing hysteresis losses in magnetic particle systems, while research to date 

has focused on minimizing hysteresis. 

4.1 Particle D’esiga. The following are the primary barriers that need to be addressed. 

l Magnetization dynamics in high-frequency magnetic fields. 

l Effects of magnetic phase transition on hysteresis heating (energy loss). 

l Identification of particle composition, size, microstructure, induction power, and 

frequency for maximum heat generation or power loss at a specified Curie temperature. 

The research described in this report would establish the science base for design and 

synthesis of nanoparticles for hysteresis heating applications. 

4.2 Polymer Processing. Magnetic particle systems with T, between 100 and 400 “C would 

be chosen for polymer processing demonstrations. Heat-transfer simulations and experiments of 

nanoparticle/polymer systems will be performed to ensure that particles are viable and optimized 

for hysteresis heating applications. 

23 
4.3 Selective Cell Death. The biological component is designed to explore the ability of 

intracellular nanoparticles to cause selective cell death. These experiments would examine how 

varying parameters such as particle size, composition, and density, as well as induction 

frequency and power level, can be used to cause selective cell death with minimal collateral 

damage. 

24 
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S BEAUDOIN 

KANSAS ST 

NATICK MA 01760-5019 

9 US ARMY RESEARCH OFC 

A CROWSON 

J CHANDRA 

H EVERETT 

J PRATER 

R SINGLETON 

G ANDERSON 

D STEPP 

D KISEROW 

J CHANG 

PO BOX 12211 

RESEARCH TRIANGLE PARK NC 

27709-2211 

1 NAVAL SURFACE WARFARE CTR 

DAHLGREN DIV CODE GO6 

DAHLGREN VA 22448 I 

41 

NO. OF 

COPIES 

1 

3 

1 

2 

2 

1 

ORGANIZATION 

NAVAL SURFACE WARFARE CTR 

TECH Lll3R4RY CODE 323 

17320 DAHLGREN RD 

DAHLGREN VA 22448 

NAVAL RESEARCH LAB 

I WOLOCK CODE 6383 

R BADALLANCE CODE 6304 

L GAUSE 

WASHINGTON DC 20375 

NAVAL SURFACE WARFARE CTR 

CRANE DIVISIQN 

M JOHNSON CODE 20H4 

LOUISVILLE KY 40214-524s 

COMMANDER 

NAVAL SURFACE WARFARE CTR 

CARDEROCK DIVISION 

R PETERSON CODE 2020 

M CRITCHFIELD CODE 1730 

BETHESDA MD 20084 

NAVAL SURFACE WARFARE CTR 

U SORATHIA 

C WILLIAMS CD 6551 

9500 MACARTHUR BLVD 

WEST BETHESDA MD 208 17 

DAVLD TAYLOR RESEARCH CT-R 

SHIP STRUCTURES 

& PROTECTION 

DEPT CODE 1702 

BETHESDA MD 20084 

DAVID TAYLOR RESEARCH CTR 

R ROCKWELL 

W PHYILLALER 

BETHESDA MD 20054-5000 

OFC OF NAVAL RESEARCH 

D SIEGEL CODE 35 1 

800 N QUINCY ST 

ARLINGTON VA 222 17-5660 
NO. OF 

COPIES 

8 

ORGANIZATION 

NAVAL SURFACE WARFARE CTR 

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 

NAVAL SEA SYSTEMS CMD 

D LIESE 

253 1 JEFFERSON DAVIS HWY 

ARLINGTON VA 22242-5 160 

NAVAL SURFACE WARFARE CTR 

M LACY CODE B02 

17320 DAHLGREN RD 

DAHLGREN VA 22448 

OFC OF NAVAL RES 

J KELLY 

800 NORTH QUINCEY ST 

ARLINGTON VA 222 17-5000 

NAVAL SURFACE WARFARE CTR 

CARDEROCK DIVISION 

R CRANE CODE 2802 

C WILLIAMS CODE 6553 

3A LEGGETT CIR 

BETHESDA MD 20054-5000 

EXPEDITIONARY WARFARE DIV N85 

F SHOUP 

2000 NAVY PENTAGON 

WASHINGTON DC 20350-2000 

AFRL MLBC 

2941 P ST RM 136 

WRIGHT PATTERSON AFB OH 

45433-7750 

AFRL MLSS 

R THOMSGN 

2179 12TH STRM 122 

WRIGHT PATTERSON AFB OH 

45433-7718 

NO. OF 

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2 

1 

1 

1 

1 

3 

2 

2 

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AFRL 

FABRAMS 

J BROWN 

BLDG 653 

2977 P ST STE 6 

WRIGHT PATTERSON AFB OH :. 

45433-7739 

AFRL MLS OL 

L COULTER 

7278 4TH ST 

BLDG 100 BAY D 

HILL AFB UT 84056-5205 

OSD 

JOINT CCD TEST FORCE 

OSD JCCD 

R WILLIAMS 

3909 HALLS FERRY RD 

VICKSBURG MS 29180-6199 

DEFENSE NUCLEAR AGENCY 

INNOVATIVE CONCEPTS DIV 

680 1 TELEGRAPH RD 

ALEXANDRIA VA 223 lo-3398 

WATERWAYS EXPERIMENT 

D SCOTT 

3909 HALLS FERRY RD SC C 

VICKSBURG MS 391 SO 

DARPA 

M VANFOSSEN 

SWAX 

L CHRISTODOULOU 

370 1 N FAIRFAX DR 

ARLINGTON VA 22203-1714 

TECH CENTER 

D OPLINGER AAR 43 1 

P SHYPRYKEVICH AAR 43 1 

ATLANTIC CITY NJ 08405 

SERDP PROGRAM OFC 

PM P2 

C PELLERIN 

B SMITH 

901 N STUART ST STE 303 

ARLINGTON VA 22203 

42 
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COPIES 

1 

1 

1 

5 

1 

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FAA 

MIL HDBK 17 CHAIR 

L ILCEWICZ 

160 I LIND AVE SW 

ANM 115N 

RESTON VA 98055 

US DEPT OF ENERGY 

OFC OF ENVIRONMENTAL 

MANAGEMENT 

P RITZCOVAN 

1990 1 GERMANTOWN RD 

GERMANTOWN MD 20874-1928 

DIRECTOR 

LLNL 

F ADDESSIO MS B2 16 

PO BOX 1633 

LOS ALAMOS NM 87545 

DIRECTOR 

LLNL 

R CHRISTENSEN 

S DETERESA 

F MAGNESS 

MFINGERMS313 

M MURPHY L 282 

PO BOX 808 

LIVERMORE CA 94550 

OAK RIDGE NATIONAL 

LABORATORY 

R M DAVIS 

PO BOX 2008 

OAK FUDGE TN 37831-6195 

OAK RIDGE NATJONAL 

LABORATORY 

C EBERLE MS 8048 

PO BOX 2009 

OAK RIDGE TN 3783 1 

OAK RIDGE NATIONAL 

LABORATORY 

C D WARREN MS 8039 

PO BOX 2009 

OAK RIDGE TN 37922 

NO. OF 

COPIES ORGANIZATION 

NIST 

R PARNAS 

J DUNKERS 

M VANLANDINGHAM MS 862 1 

J CHIN MS 8621 

D HUNSTON MS 8543 

J MARTIN MS 8621 

D DUTHINH MS 8611 

100 BUREAU DR 

GAITHERSBURG MD 20899 

1 LOCKHEED MARTIN MISSILES 

& FIRE CONTROL 

R TAYLOR 

PO BOX 650003 M S WT 93 

DALLAS TX 75265-0003 

1 HYDROGEOLOGIC INC 

SERDP ESTCP SPT OFC 

S WALSH 

1155 HERNDON PKWY STE 900 

HERNDON VA 20170 

3 DIRECTOR 

SANDIA NATIONAL LABS 

APPLIED MECHANICS DEPT 

DIV 8241 

J HANDROCK 

YRKAN 

J LAUFFER 

PO BOX 969 

LIVERMORE CA 94550-0096 

3 NASA LANGLEY RSCH CTR 

AMSRL vs 

W ELBER MS 266 

F BARTLETT JR MS 266 

G FARLEY MS 266 

HAMPTON VA 2368 l-000 1 

1 NASA LANGLEY RSCH CTR 

T GATES MS 188E 

HAMPTON VA 23661-3400 

1 USDOT FEDERAL RAILRD 

M FATEH RDV 3 1 

WASHINGTON DC 20590 

43 
NO. OF 

COPIES 

1 

2 

NO. OF 

COPIES ORGANIZATION ORGANIZATION 

1 FHWA 

E MUNLEY 

6300 GEORGETOWN PIKE 

MCLEAN VA 22101 

COMPOSITE MATERIALS JNC 

C RILEY 

14530 S ANSON AVE 

SANTA FE SPRINGS CA 90670 

CENTRAL INTLLGNC AGNCY 

OTI WDAG GT 

W L WALTMAN 

PO BOX 1925 

WASHINGTON DC 20505 

I COMPOSIX 

D BLAKE 

L DIXON 

120 0 NEILL DR 

HEBRUN OHIO 43025 

MARINE CORPS INTLLGNC ACTVTY 

D KOSITZKE 

3300 RUSSELL RD STE 250 

QUANTICO VA 22 134-5011 

I 4 CYTEC FIBERITE 

RDUNNE 

D KOHL1 

RI GILL10 

R MAYHEW 

1300 REVOLUTION ST 

HAVRE DE GRACE MD 2 1078 

I DIRECTOR 

NATIONAL GRND JNTLLGNC CTR 

IANG TM-J 

220 SEVENTH ST NE 

CHARLOTTESVILLE VA 

229023396 

2 SIMTJLA 

J COLTMAN 

R HUYETT 

10016 S 51ST ST 

1 DIRECTOR PHOENIX AZ 85044 

DEFENSE INTLLGNC AGNCY 

TA5 

K CRELLING 

WASHINGTON DC 203 10 

SIOUX MFG 

B KRIEL 

PO BOX 400 

FT TOT-TEN ND 58335 

1 GRAPHITE MASTERS INC 

J WILLIS 

3815 MEDFORD ST 

LOS ANGELES CA 90063-1900 

PROTECTION MATERIALS INC 

M MILLER 

F CRILLEY 

14000 NW 58 CT 

I ADVANCED GLASS FIBER YARNS MIAMI LAKES FL 33014 

T COLLINS 

281 SPRING RUN LANE STE A 

DOWNINGTON PA 19335 

3 FOSTER MILLER 

J J GASSNER 

M ROYLANCE 

WZUKAS 

195 BEAR HILL RD 

WALTHAM MA 02354-l 196 

COMPOSITE MATERJALS INC 

D SHORTT 

19105 63 AVE NE 

PO BOX 25 

ARLINGTON WA 98223 

1 

ROM DEVELOPMENT CORP 

ROMEARA 

136 SWINEBURNE ROW 

BRICK MARKET PLACE 

NEWPORT RI 02840 

1 

1 COMPOSITE MATERIALS INC 

R HOLLAND 

11 JEWEL CT 

ORlNDA CA 94563 

44 
NO. OF 

COPIES 

2 

1 

2 

1 

2 

1 

I 

2 

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TEXTRON SYSTEMS 

T FOLTZ 

M TREASURE 

201 LOWELL ST 

WILMINGTON MA 08870-2941 

JPS GLASS 

L CARTER 

PO BOX 260 

SLATER RD 

SLATER SC 29683 

0 GARA HESS & EISENHARDT 

M GILLESPIE 

9113 LESAINT DR 

FAIRFIELD OH 45014 

MILLIKEN RSCH CORP 

HKUHN 

M MACLEOD 

PO BOX 1926 

SPARTANBURG SC 29303 

CONNEAUGHT INDUSTRJES MC 

J SANTOS 

PO BOX 1425 

COVENTRY RI 02816 

BATTELLE NATICK OPNS 

J CONNORS 

B HALPIN 

209 W CENTRAL ST STE 302 

NATICK MA 01760 

BATTELLE NW DOE PNNL. 

T HALL MS K231 

BATTELLE BLVD 

RICHLAND WA 99352 

ARMTEC DEFENSE PRODUCTS 

S DYER 

85 901 AVE 53 

PO BOX 848 

COACHELLA CA 92236 

GLCC MC 

JRAY 

M BRADLEY 

103 TRADE ZONE DR STE 26C 

WEST COLUMBIA SC 29170 

NO. OF 

COPIES 

3 

2 

1 

ORGANIZATION 

PACIFIC NORTHWEST LAB 

M SMITH 

G VAN ARSDALE 

R SHIPPELL 

PO BOX 999 

RLCHLAND WA 99352 

AMOCO PERFORMANCE 

PRODUCTS 

M MICHNO JR 

J BANISAUKAS 

4500 MCGINNIS FERRY RD 

ALPHARETTA GA 30202-3944 

SAIC 

M PALMER 

2109AIRPARKRDSE 

ALBUQUERQUE NM 87106 

SAIC 

G CHRYSSOMALLIS 

3800 W XOTH ST STE 1090 

BLOOMINGTON MN 5543 1 

&%I CORPORATION 

T G STASTNY 

PO BOX 126 

HUNT VALLEY MD 21030-0126 

APPLIED COMPOSITES 

W GRISCH 

333 NORTH SIXTH ST 

ST CHARLES IL 60174 

ALLIANT TECHSYSTEMS MC 

J CONDON 

E LYNAM 

JGERHARD 

WV01 16 STATE RT 956 

POBOX210 

ROCKET CENTER WV 

26726-02 10 

CUSTOM ANALYTICAL 

ENG SYS INC 

A ALEXANDER 

13000 TENSOR LANE NE 

FLINTSTONE MD 2 1530 

45 
NO. OF 

COPIES ORGANIZATION 

8 ALLIANT TECHSYSTEMS INC 

C CANDLAND MN1 1 2830 

C AAKHUS MN1 1 2830 

B SEE MN1 1 2439 

N VLAHAKUS MN11 2145 

R DOHRN MN1 1 2830 

S HAGLUND MN1 1 2439 

M HISSONG MN1 12830 

D KAMDAR MN1 12830 

600 SECOND ST NE 

HOPKINS MN 55343-8367 

1 PROJECTILE TECHNOLOGY INC 

5 15 GILES ST 

HAVRE DE GRACE MD 2 1078 

I 2 LORAL VOUGHT SYSTEMS 

G JACKSON 

K COOK 

170 1 W MARSHALL DR 

GRAND PRAIRIE TX 7505 1 

5 AEROJET GEN CORP 

D PILLASCH 

T COULTER 

C FLYNN 

D RUBAREZUL 

M GREINER 

1100 WEST HOLLYVALE ST 

AZTJSA CA 91702-0296 

3 HEXCEL INC 

R BOE 

F POLICELLI 

J POESCH 

PO BOX 98 

MAGNA UT 84044 

I HERCULES INC 

HERCULES PLAZA 

WILMINGTON DE 19894 

1 BRIGS COMPANY 

J BACKOFEN 

2668 PETERBOROUGH ST 

HERNDON VA 2207 J-2443 

NO. OF 

COPIES 

1 

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ZERNOW TECHNICAL SERVICES 

LZERNOW ’ 

425 W BONITA AVE STE 208 

SAN DIMAS CA 9 1773 

OLIN CORPOJ&4TION 

FLINCHBAUGH DIV 

E STEINER 

B STEWART 

PO BOX 127 

RED LION PA 17356 

F 

OLIN CORPORATION 

L WHITMORE 

10 10 1 NINTH ST NORTH 

ST PETERSBURG FL 33702 

GKN AEROSPACE 

D OLDS 

15 STERLING DR 

WALLINGFORD CT 06492 

SIKORSKY AIRCR4FT 

G JACARUSO 

T CARSTENSAN 

BKAY 

S GARBO MS S33OA 

J ADELMANN 

6900 MAIN ST 

PO BOX 9729 

STRATFORD CT 06497-9729 

PRATT & WHITNEY 

D HAMBRICK 

400 MAIN ST MS 114 37 

EAST HARTFORD CT 06 108 

AEROSPACE CORP 

G HAWKINS M4 945 

2350 E EL SEGUNDO BLVD 

EL SEGUNDO CA 90245 

CYTEC FIBERITE 

MLIN 

W WEB 

1440 N KRAEMER BLVD 

ANAHEIM CA 92806 

46 
NO. OF 

COPIES 

1 

w 1 

2 

2 

1 

1 

1 

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ORGANIZATION 

HEXCEL 

T BITZER 

117 11 DUBLIN BLVD 

DUBLIN CA 94568 

BOELNG 

R BOHLMANN 

PO BOX 5 16 MC 5021322 

ST LOUIS MO 63 166-05 16 

BOEING DFNSE & SPACE GP 

w HAMMOND s 4x55 

J RUSSELL S 4X55 

PO BOX 3707 

SEATTLE WA 98 124-2207 

BOEING ROTORCRAFT 

P MINGURT 

P HANDEL 

800 B PUTNAM BLVD 

WALLMGFORD PA 19086 

BOEING 

DOUGLAS PRODUCTS DIV 

L J HART SMITH 

3855 LAKEWOOD BLVD 

DSOO 0019 

LONG BEACH CA 90846-000 1 

LOCKHEED MARTIN 

S REEVE 

8650 COBB DR 

D7362MZ0648 

MARIETTA GA 30063-0648 

LOCKHEED MARTIN 

SKUNK WORKS 

D FORTNEY 

1011 LOCKHEED WAY 

PALMDALE CA 93599-2502 

LOCKHEED MARTIN 

R FIELDS 

1195 IRWIN CT 

WlNTER SPRINGS FL 32708 

MATERIALS SCIENCES CORP 

B W ROSEN 

500 OFC CENTER DR STE 250 

FT WASHINGTON PA 19034 

47 

NO. OF 

COPIES 

1 

2 

3 

4 

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NORTHRUP GRUMMAN CORP 

ELECTRONIC SENSORS 

& SYSTEMS DIV 

E SCHOCH MS V 16 

1745A W NURSERY RD 

LINTHICUM MD 2 1090 

NORTHROP GRUMMAN 

ENVIRONMENTAL PROGRAMS 

R OSTERMAN 

A YEN 

8900 E WASHINGTON BLVD 

PICO RIVERA CA 90660 

UDLP 

D MARTIN 

PO BOX 359 

SANTA CLARA CA 95052 

UDLP 

G THOMAS 

PO BOX 58123 

SANTA CLARA CA 95052 

UDLP 

R BARRETT MAIL DROP M53 

V HORVATICH MAIL DROP M53 

328 W BROKAW RD 

SANTA CLARA CA 95052-0359 

UDLP 

GROUND SYSTEMS DIVISION 

M PEDRPLZZI MAIL DROP NO9 

A LEE MAIL DROP Nl 1 

M MACLEAN MAJL DROP NO6 

1205 COLEMAN AVE 

SANTA CLARA CA 95052 

UDLP 

R BRYNSVOLD 

P JANKE MS 170 

T GIOVANE’ITI MS 236 

B VAN WYK MS 389 

4800 EAST RJVER RD 

MINNEAPOLIS MN 55421-1498 

GDLS DIVISION 

D BARTLE 

PO BOX 1901 

WARREN MI 48090 
NO. OF 

COPIES 

2 

1 

5 

2 

ORGANIZATION 

GDLS 

D REES 

M PASIK 

PO BOX 2074 

WARREN MI 48090-2074 

GDLS 

MUSKEGON OPERATIONS 

W SOMMERS JR 

76 GETTY ST 

MUSKEGON MI 49442 

GENERAL DYNAMICS 

AMPHIBIOUS SY S 

SURVIVABILITY LEAD 

G WALKER 

991 ANNAPOLIS WAY 

WOODBRIDGE VA 22 19 1 

INST FOR ADVANCED 

TECH 

T KIEHNE 

HFAIR 

P SULLIVAN 

W REINECKE 

I MCNAB 

4030 2 W BRAKER LN 

AUSTIN TX 78759 

CIVIL ENGR RSCH FOUNDATION 

PRESIDENT 

H BERNSTEIN 

R BELLE 

1015 15TH ST NW STE 600 

WASHINGTON DC 20005 

ARROW TECH ASS0 

1233 SHELBURNE RD STE D 8 

SOUTH BURLINGTON VT 

05403-7700 

R EICHELBERGER 

CONSULTANT 

409 W CATHERINE ST 

BEL AIR MD 21014-3613 

UCLA MANE DEPT ENGR IV 

HTHAHN 

LOS ANGELES CA 90024- 1597 

NO. OF 

COPIES 

2 

1 

1 

1 

1 

1 

1 

ORGANIZATION 

UNIV OF DAYTON 

RESEARCH JNST 

RYKIM 

AKROY 

300 COLLEGE PARK AVE 

DAYTON OH 45469-0168 

MIT 

P LAGACE 

77 MASS AVE 

CAMBRIDGE MA 01887 

IIT RESEARCH CENTER 

D ROSE 

201 MILL ST 

ROME NY 13440-6916 

GA TECH RSCH MST 

GA INST OF TCHNLGY 

P FRIEDERICH 

ATLANTA GA 30392 

MICHIGAN ST UNIV 

MSM DEPT 

R AVERILL 

3515 El3 

EAST LANSING MI 48824- 1226 

UNIV OF KENTUCKY 

L PENN 

763 ANDERSON HALL 

LEXINGTON KY 40506-0046 

UNIV OF WYOMING 

D ADAMS 

PO BOX 3295 

LARAMIE WY 82071 

UNIV OF UTAH 

DEPT OF MECH & 

INDUSTRIAL ENGR 

S SWANSON 

SALTLAKECITYUTX4112 

PENN STATE UNIV 

R MCNITT 

C BAKIS 

2 12 EARTH ENGR SCIENCES BLDG 

UNIVERSITY PARK PA 16802 

48 
NO. OF 

COPIES 

1 

1 

. 

I 

ORGANIZATION 

PENN STATE UNIV 

R S ENGEL 

245 HAMMOND BLDG 

UNIVERSITY PARR PA 16801 

PURDUE UNIV 

SCHOOL OF AERO & AS-FRO 

CTSUN 

W LAFAYETTE l-N 47907-l 282 

STANFORD U-NIV 

DEPT OF AERONAUTICS 

& AEROBALLISTICS 

S TSAI 

DURANT BLDG 

STANFORD CA 94305 

UNTV OF DAYTON 

J M WHITNEY 

COLLEGE PARR AVE 

DAYTON OH 45469-0240 

UNIV OF DELAWARE 

CTR FOR COMPOSITE MTRLS 

J GILLESPIE 

M SANTARE 

G PALMESE 

S YARLAGADDA 

S ADVANI 

D HEIDER 

D KUKICH 

201 SPENCER LABORATORY 

NEWARK DE 19716 

UNIV OF ILLINOIS AT 

URBANA CHAMPAIGN 

NATIONAL CENTER 

FOR COMPOSITE 

MATERIALS RESEARCH 

J ECONOMY 

216 TALBOT LABORATORY 

104 S WRIGHT ST 

URBANA IL 61801 

NORTH CAROLINA STATE U-NIV 

CIVIL ENGINEERING DEPT 

W RASDORF 

PO BOX 7908 

RALEIGH NC 27696-7908 

NO. OF 

COPIES 

3 

3 

1 

1 

ORGANIZATION 

THE UNIV OF 

TEXAS AT AUSTIN 

CTR FOR ELECTROMECHANKS 

J PRICE 

A WALLS 

J RITZMILLER 

10100 BURNET RD 

AUSTIN TX 78758-4497 

VA POLYTECHNICAL 

INST & STATE UNIV 

DEPT OF ESM 

MWHYER 

K REIFSNIDER 

R JONES 

BLACKSBURG VA 2406 I-02 19 

UNIV OF MARYLAND 

DEPT OF AEROSPACE ENGNRNG 

A J VIZZIM 

COLLEGE PARR MD 20742 

DREXEL UNIV 

ASDWANG 

32ND & CHESTNUT ST 

PHILADELPHIA PA 19104 

SOUTHWEST RSCH INST 

ENGR & MATL SCIENCES DIV 

J RIEGEL 

6220 CULEBRA RD 

PO DRAWER 28510 

SAN ANTONIO TX 7X228-05 10 

ABERDEEN PROVING GROUND 

US ARMY MATERIEL 

SYSTEMS ANALYSIS 

P DIETZ 

392 HOPKINS RD 

AMXSY TD 

APG MD 21005-5071 

DIRECTOR 

US ARMY RESEARCH LAB 

AMSRLOPAPL 

APG MD 2 1005-5066 

49 
NO. OF NO. OF 

COPIES ORGANIZATION COPIES ORGANIZATION 

ABERDEEN PROVING GROUND (CONT) 

106 DIR USARL 

AMSRL CI 

AMSRL CT H 

w STuREK 

AMSRL CI S 

AMARK 

AMSRL CS IO FI 

M ADAMSON 

AMSRL SL B 

J SMITH 

AMSRL SL BA 

AMSRL SL BL 

D BELY 

R HENRY 

AMSRL SL BG 

AMSRL SL I 

AMSRL WM B 

A HORST 

E SCHMIDT 

AMSRL WM BA 

F BRANDON 

AMSRL WM BC 

I’ PLOSTlNS 

D LYON 

J NEWILL 

S WILKERSON 

A ZIELINSKI 

AMSRL WM BD 

B FORCH 

R FIFER 

R PESCE RODRIGUEZ 

B RICE 

AMSRL WM BE 

C LEVERITT 

D KOOKER 

AMSRL WM BR 

C SHOEMAKER 

J BORNSTEIN 

AMSRL WM M 

D VIECHNICKI 

G HAGNAUER 

J MCCAULEY 

B TANNER 

AMSRL WM MA 

R SHUFORD 

P TOUCHET 

N BECK TAN 

ABERDEEN PROVING GROUND (CONT) 

AMSRL WM MA 

D FLANAGAN 

L GHIORSE 

DHARRIS 

S MCKNIGHT 

P MOY 

P PATTERSON 

G RODRIGUEZ 

A TEETS 

RYIN 

AMSRL WM MB 

BFINK 

J BENDER 

T BLANAS 

T BOGETTI 

R BOSSOLI 

L BURTON 

K BOYD 

S CORNELISON 

P DEHMER 

R DOOLEY 

W DRYSDALE 

G GAZONAS 

S GHIORSE 

D GRANVILLE 

D HOPKINS 

C HOPPEL 

D HENRY 

R KASTE 

M KLUSEWITZ 

M LEADORE 

R LIEB 

E RIGAS 

J SANDS 

D SPAGNUOLO 

W SPURGEON 

J TZENG 

E WETZEL 

AMSRL WM MB ALC 

A FRYDMAN 

AMRSL WM MC 

J BEATTY 

E CHIN 

J MONTGOMERY 

A WERECZCAK 

J LASALVIA 

J WELLS 

50 
NO. OF 

COPIES ORGANIZATION 

ABERDEEN PROVING GROUND (CONT.) 

AMSRL WM MD 

W ROY 

S WALSH 

AMSRL WM T 

B BURNS 

AMSRL WM TA 

W GILLICH 

T HAVEL 

J RUNYEON 

M BURKINS 

E HORWATH 

B GOOCH 

W BRUCHEY 

AMSF!L WM TC 

R COATES 

AMSRL WM TD 

A DAS GUPTA 

T HADUCH 

T MOYNIHAN 

F GREGORY 

A RAJENDRAN 

M RAFTENBERG 

M BOTELER 

T WEERASOORIYA 

D DANDEKAR 

A DIETRICH 

AMSRL WM TE 

A NIILER 

J POWELL 

Aia3R.L SS SD 

H WALLACE 

AMSRL SS SE R 

R CHASE 

AMSRL SS SE DS 

R REYZER 

R ATKINSON 

AMSRL SE L 

R WEINRAUB 

J DESMOND 

D WOODBURY 

51 
NO. OF 

COPIES ORGANIZATION 

1 LTD 

R MARTIN 

MERL 

TAMWORTH RD 

HERTFQRD SG13 7DG 

UK 

1 SMC SCOTLAND 

PWLAY 

DERA ROSYTH 

ROSYTH ROYAL DOCKYARD 

DUNFERMLINE FIFE KY 112XR 

UK 

1 CIVIL AVIATION 

ADMINSTRATION 

T GOTTESMAN 

PO BOX 8 

BEN GUIUON INTERNL AIRPORT 

LOD 70150 ISRAEL 

NO. OF 

COPIES 

2 

1 

1 

1 

1 AEROSPATIALE 

S ANDRE 

A BTE CC RTE MD132 

3 16 ROUTE DE BAYONNE 

TOULOUSE 3 1060 

FRANCE 

1 DAIMLER BENZ AEROSPACE 

J BAUER 

D 81663 MUNCHEN 

MUNICH 

GERMANY 

3 DRA FORT HALSTEAD 

P N JONES 

D SCOTT 

M HINTON 

SEVEN OAKS KENT TN 147BP 

UK 

1 DEFENSE RESEARCH ESTAB 

VALCARTIER 

F LESAGE 

COURCELETTE QUEBEC COA 

IRO CANADA 

52 

1 

1 

1 

ORGANIZATION 

ROYAL MILITARY COLLEGE OF 

SCIENCE SHRIVENHAM 

D BULMAN 

B LAWTON 

SWINDON WILTS SN6 8LA 

UK 

SWISS FEDERAL ARMAMENTS 

WKS 

W LAN2 

ALLMENDSTRASSE 86 

3602 THUN 

SWITZERLAND 

ISRAEL INST OF 

TECHNOLOGY 

S BODNER 

FACULTY OF MECHANICAL ENGR 

HAIFA 3200 ISRAEL 

DSTO MATERIALS RESEARCH LAB 

NAVAL PLATFORM WLNERABILITY 

SHIP STRUCTURES & MTRLS DIV 

N BURMAN 

PO BOX 50 

ASCOT VALE VICTORIA 

AUSTRALIA 3032 

ECOLE ROYAL MILITAIRE 

E CELENS 

AVE DE LA RENAISSANCE 30 

1040 BRUXELLE 

BELGIQUE 

DEF RES ESTABLISHMENT 

VALCARTIER 

A DUPUIS ._I. ,,

2459 BOULEVARD PIE XI NORTH 

VALCARTIER QUEBEC 

CANADA 

PO BOX 8800 COURCELETTE 

GOA IRO QUEBEC CANADA 

INSTITUT FRANC0 ALLEMAND 

DE RECHERCHES DE SAINT LOUIS 

DE M GIRAUD 

5 RUE DU GENERAL CASSAGNOU 

BOITE POSTALE 34 

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GROUND 

I CREWTHER 

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RAFAEL 

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ALJTH 

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53 
54 
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REPORT DOCUMENTATION PAGE Form Approved 

OMB No. 07W-0188 

anoslnlctlues 

Recommendations for Research 

Bruce K. Fink, Sluidhar Yarlagadda, John Q. Xiao, Gary H. Laverty, and 

John W. Gillespie, Jr. 

U.S. Army Research Laboratory 

Al-l-N: AMSRLrWM-MB 

Aberdeen Proving Ground, MD 2 10055069 

REPORT NUMBER 

ARL-TR-2365 

i2a. DISTRIBUTION/AVAlLABlLlTY STATEMENT 

Approved for public release; distribution is unlimited. 

12b. DISTRIBUTION CODE 

13. ABSTRACT(Maximum 200 words) 

This report presents the concept for a multidisciplinary research program aimed at establishing the science base for 

he design and synthesis of magnetic nanoparticles for hysteresis heating, with potential applications ranging from novel 

:omposites processing techniques to alternative cancer treatments. Magnetic materials are used in a wide range of 

applications and designed for maximum efficiency or minimized hysteresis loss. The uniqueness of this project is that, 

while considerable work has been aimed at reducing hysteresis losses, the converse effect (i.e., increasing hysteresis 

.osses and therefore heat generation) has not been fully studied. Hysteresis-based heating has several advantages over 

conventional heating techniques, including the fact that it is a very rapid and noncontact process. In addition, the Curie 

temperature of magnetic materials can also be used as a means of “smart” thermal control. Exploratory basic research 

through ongoing programs at the U.S. Army Research Laboratory (ARL) has established the feasibility of Curie 

temperature control and demonstrated the effects of particle size, frequency, and stoichiometry on hysteresis losses. The 

following scientific barriers are addressed in this report: magnetization dynamics in high-frequency magnetic fields, the 

effects of magnetic phase transition on hysteresis heating, and the dimensional dependence of Curie temperature in 

nanoparticles. If carried out, the research program outlined in this report would establish the science base for the design 

and synthesis of nanoparticles for hysteresis heating applications. 

14. SUBJECT TERMS 

fiber optics sensors, composite materials, integral armor, resin nansfer molding 

15. NUMBER OF PAGES 

59 

16. PRICE CODE 

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OF REPORT 

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