CO4-1

Structural Change of Surfactant Micelles by Ion Capturing

K. Hara, T. Yanagino, T. Miyazaki, S. Yoshioka, Y. Oba1,
N. Sato1 and M. Sugiyama1
Department of Applied Quantum Physics and Nuclear
Engineering, Kyushu University
1
Research Reactor Institute, Kyoto University
INTRODUCTION: Surfactants show interesting properties and are also useful for various kinds of applications. Among them, the authors have been interested in
and investigating their heavy-metal capturing property
intending to make use of their properties for environment purification. In such an investigation, the nanoscale structural examinations of the surfactants at several conditions are well-known to be essential because theheavy-metal capturing always follows their nano-structural changes. In the present study, the authors have investigated the nano-structural change of a surfactant,sodium oleate, in heavy water before and after the floatation treatments.

Fig. 1.

The SANS profiles of 30 mM sodium
oleate in heavy water at several pH’s
measured by KUR-SANS system.

Fig. 2.

The SANS profiles of 30 mM sodium oleate in heavy water: before (), after ()capturing cupper ion and after the subsequent floatation treatment at pH=10 ()measured by KUR-SANS system.

Fig. 3.

The SANS profiles of 30 mM sodium
oleate in heavy water after the floatation
treatment at several pH’s measured by
KUR-SANS system.

EXPERIMENTS: The 30 mM heavy-water solution of
sodium oleate (SO) at several pH’s (adjusted by adding
HCl and NaOH) were prepared and sealed into respective quartz cells, of which the small angle neutron scattering (SANS) profiles (Fig.1) were measured after
having been left intact for 24 hours at room temperature.
The SANS experiments were performed with a KURSANS system installed at Kyoto University Reactor,
Kumatori, Osaka, Japan. In addition, prepared were the
30 mM SO H2O solutions containing 5 mM copper ion,of which the pH’s were adjusted at several values after
the addition of the cupric ion. The SANS profiles werealso measured for some of the Cu-added SO solutions atseveral pH’s, one of which is shown as the SANS profile plotted with  in Fig. 2. Besides, the SANS profilesof the Cu-added SO solutions at several pH’s were
measured after the 5 min floatation treatments utilizing a
glass filter with 40~50 m pore-size and an air pumpwith 7.8 kPa discharge pressure (the SANS profile plotted with  in Fig. 2 and Fig. 3).
RESULTS: As shown in Fig. 1, the SANS profile exhibits a distinctive peak in a pH≧8 range, indicating a distinctive structure in the SO solution. Their SANS profiles show drastic changes with the addition of Cu ion to
the SO solution, as shown in Fig. 2, demonstrating the
emergence of the larger structure. The SANS profiles
are also largely affected by the floatation treatments asshown in Fig. 3.

界面活性剤ミセル・ゲルの重金属吸着に伴うナノ構造・
共同通常
ダイナミクス変化に関する研究(九大院·工)原 一広、柳野 智、宮崎智博、吉岡 聰 (京大·原子炉)大場洋次郎、佐藤信浩、
杉山正明

採択課題番号 24007

DMSO-Assisted Grafting of Acrylamide onto PET Film by γ Irradiation

EXPERIMENTS: The dry PET films weighing Wpristine
were soaked in DMSO for 0.5 h at different temperatures(from 100 to 160°C). After withdrawing the PET films
from DMSO, excess liquid on the surface was removedby blotting between filter paper. The DMSO-treated PET
films were taken into glass bottles containing different
concentration (25, 40, 50 and 70 wt %) of AAm aqueous
solutions. FeCl3 at a constant concentration (1 wt %) was
added after 24 h to the AAm solutions to minimize
homopolymer formation. The contents of the glass bottles were then irradiated with different doses (20, 50, 70,
100 kGy) of γ rays with a dose rate of 1.0 kGy/h in air(γ-ray irradiation of the PET films was carried out at the60
Co γ-ray irradiation facility of Research Reactor Institute, Kyoto University). The obtained grafted films were
washed in distilled water at 60°C for 24 h to remove thehomopolymers. Then the films were dried in a vacuum
oven at 60°C for 24 h and were weighed (WAAm grafted ).
The graft yield was determined by the percent increase in
the weight as follows:δWAAm grafted (%) = (WAAm grafted - Wpristine ) / Wpristine×100 .
RESULTS: When γ irradiation of pristine PET films was
carried out as they were soaked in an AAm solution no
grafting of AAm was observed which might be due tolow diffusion of AAm solution into the polymer matrix.
Therefore PET films were treated with DMSO prior tografting, to promote the diffusion and sorption of AAm
and subsequent grafting of AAm on PET by γ irradiation.
Grafting of AAm onto DMSO-treated films were studied

198–203.
[2] M. Nasef, J. Appl. Polym. Sci., 77 (2000) 1003–1012.
[3] X. Ping et al., Radiat. Phys. Chem. 80 (2011)632-637.
40
35
30
25
20
15
10
5
0

15
Graft Yield (%)

INTRODUCTION: Poly(ethylene terephthalate) (PET)
is a polymer which is widely used in packaging, fiber,
and engineering applications due to its good mechanicalstrength and relatively lower production cost. Certain
desirable properties such as hydrophilicity, ions adsorption can be imparted to PET film by grafting with different functional monomers. γ ray induced grafting of acrylic acid, styrene, n-butyl acrylate on PET films have beenstudied previously [1, 2, 3]. However, to the best of ourknowledge, no detailed study has been reported on the γ
ray induced graft copolymerization of acrylamide (AAm)onto PET films. In the present work grafting of AAm on
PET film by γ irradiation was studied by using dimethyl
sulfoxide (DMSO) as a swelling agent.

REFERENCES:[1] M. Kattan et al., J. Appl. Polym. Sci., 102 (2006)

10
5
0
-5

-10
60
110
160
210
DMSO Pretreatment Temperature ( °C)

Fig. 1. Weight gain (-☓- after soaking in DMSO for 0.5 h,-◯- after soaking in 50 wt % AAm solution for 24 h) andgraft yield (-●- for 50 wt % monomer concentration, 50
kGy dose at dose rate 1 kGy/h in presence of 1 wt %FeCl3) against DMSO treatment temperature.
20
Graft Yield (%)

Department of Applied Quantum Physics and Nuclear
Engineering, Kyushu University
1Research Reactor Institute, Kyoto University

under different conditions to investigate the effects of
DMSO treatment temperature, monomer concentrationand total dose on graft yield which are presented inFig. 1, Fig. 2 and Fig. 3 respectively.

15
10
5
0
0

20
40
60
Concentration of Acrylamide (%)

80

Fig. 2. Effect of monomer concentration on grafting of
AAm for 140 °C DMSO treatment temperature, 50 kGydose at dose rate 1 kGy/h in presence of 1 wt % FeCl3.
15Graft Yield (%)

N. Rahman, N. Sato1, S. Yoshioka, M. Sugiyama1,
K. Hara and H. Okabe

Weight Gain (%)

CO4-2

10
5
0
0

50

100

150

Dose (kGy)

Fig. 3. Effect of dose on grafting of AAm for 140 °C
DMSO treatment temperature, 50 wt % AAm concentration at dose rate 1 kGy/h in presence of 1 wt % FeCl3.

採択課題番号 2410
KUR-SANS を用いたエラストマーの中性子小角散乱観測（九大院·工）Nazia Rahman、柳野 智、宮崎智博、吉岡 聰、原 一広、岡部弘高（京大·原子炉）佐藤信浩、杉山正明

共同通常

Mössbauer Spectroscopy of Multiferroic Iron Oxides
in Applied Magnetic Field

S. Nakamura, Y. Kobayashi1, S. Kitao1 and M. Seto1

Department of Science and Engineering,
Teikyo University
1
Reserch Reactor Institute, Kyoto University
INTRODUCTION: Recently multiferroic properties ofpolar iron oxides have been extensively investigated. Inorder to clarify the mechanism of the multiferroicity,
investigations using microscopic and dynamic probes are
required. The 57Fe Mössbauer spectroscopy is one of theappropriate probes. Especially the quadrupole splitting isvery sensitive to the local environment around Fe ionsand will provide useful information. Here we report the
Mössbauer spectroscopy in applied magnetic field of themultiferroic oxide CuFeO2.
The delafossite CuFeO2 is an antiferromagnet on
triangular lattice [1]. At 4.2K, the magnetic structurechanges with applied magnetic field as 4-sublattice
antiferromagnet (up to 7T), incommensurate properscrew spin structure (7 ~ 12T) where ferroelectricity
appears(multiferroic
state),
and5-sublattice
antiferromagnet (above 12T) [2,3]. We have measured thecorresponding Mössbauer spectra in applied magnetic
field and found a change of the quadrupole splitting in
the multiferroic state.
EXPERIMENTS: The single crystal of CuFeO2 wasprovided by Dr. Noriki Terada, National Institute forMaterials Science. The c-plane disk of 3.5mm diameterand 40µm thickness was used as an absorber. The 57Fe
Mössbauer spectroscopy was conducted in conventionaltransmission geometry by using 57Co-in-Rh (50mCi) as
the γ ray source. The spectra were measured at 4.2K inapplied magnetic field up to 14T. The Doppler velocity
was calibrated by using Fe metal foil. Lorentzian line
shapes were assumed for the analysis.
RESULTS: In Fig.1, Mössbauer spectra of CuFeO2 at
4.2K in applied magnetic field are shown. The
quadrupole coupling constant (e2qQ/2) is 0.63 mm/s
under zero magnetic field. The value is three times larger
than that expected from the structure, which may be dueto the spin-orbit interaction. At H=5T, the spectrum iscomposed of two subspectra corresponding to upmoment and down-moment with intensity ratio of 1:1,
which represents to the 4-sublattice antiferromagnetic
state. The e2qQ/2 is 0.61 mm/s and remain unchanged. At
H=8T, the spectrum is composed of three subspectra
corresponding to the moments with the angles of about
30°, 80°, and 160° from the H-direction. Thisconfiguration represents the incommensurate properscrew spin structure. It is noted that the e2qQ/2’s are 0.57,
0.52, and 0.54 mm/s, respectively, and the all decrease
noticeably in the multiferroic state. At H=14T, thespectrum is again composed of two subspectra
corresponding to up-moment and down-moment withintensity ratio of 3:2, which represents the 5-sublattice
antiferromagnetic state. The e2qQ/2 recover to the valueof 0.61 mm/s. We consider that the decrease of the
e2qQ/2 in the multiferroic state is related to the spin-orbit
interaction .

Absorption rate (%)

CO4-3

-2
0
2
4
6
8
10
12

H=0

0
2
4
6

H=5T

8
0
2
4

H=8T

6

0
2
4
6
-12

H=14T
-8

-4

0
4
v (mm/s)812Fig. 1. Môssbauer spectra of CuFeO2 at 4.2K inapplied magnetic field.

REFERENCES:[1] M. Mekata, et al., J. Phys. Soc. Jpn. 62 (1993) 4474.
[2] N. Terada, et al., Phys. Rev. B 78 (2008) 014101.
[3] N. Terada, et al., J. Phys. Soc. Jpn. 77 (2008) 054701.

採択課題番号24011 マルチフェロイック鉄酸化物の磁場中メスバウアー分光（帝京大・理工）中村真一（京大・原子炉）瀬戸誠、北尾真司、小林康浩

共同通常CO4-4

Broadband Spectroscopy of Nanoporous-Gold Promoter

S. Kuwano-Nakatani, Y. H. Han , T. Takahashi1 andT. Awano

1

Faculty of Engineering, Tohoku Gakuin University
Research Reactor Institute, Kyoto University

0.8

0.6
42nm
33nm
25nm
20nm
11nm

0.4

0.2

0

10-3

10-2
10PHOTON ENERGY(eV)

100

Fig. 1. Reflectivity spectra of NPG membranes onquartz substrates. Average pore diameters of the fivesamples with diameter on the order of 42 nm to 11 nm
are shown in the NIR-UV figure.
100

10-1

Im(ε-1)INTRODUCTION: It is well known that bulk Au is
inert. However, Au nanoparticles with several-nanometer-scale sizes are catalytically active for several chemical reactions such as the decomposition offormaldehyde and oxidation of CO[1]. The catalytic activity depends on the size of nanoparticles. The nanoparticles with diameters less than 3–5 nm show the highest
activity for oxidation. Nanoporous Au (NPG) with 10–50
nm pore size also shows catalytic activity for oxidation.
Recently, TiO2 is being widely used for photocatalysis ofvarious materials. TiO2 has a different activity with crystal structure for different wavelengths. It has been reported that composite materials of TiO2 with Au or Pt
nanoparticles enhance TiO2 catalytic activity. TiO2 plays
an active role in the decomposition of water to generate
OH radicals. It is supposed that the plasmonic electromagnetic effect of Au or Pt enhances the catalytic activityof TiO2. In addition, since pores of NPG are able to trap
the TiO2 particles, NPG seems to be a photocatalytic
nanocomposite because of enhancement of the catalytic
activity by the electromagnetic effect. We have found that
NPG acts as a promoter to produce OH radicals using
TiO2. We report optical properties of NPG and NPG/TiO2
in this paper to investigate electromagnetic and plasmonic origin of the promotor effect.

REFLECTIVITY

1

42nm
33nm
25nm
20nm
11nm

10-2

10-3

10-4

EXPERIMENTS: NPG films were obtained by nitricacid etching of Ag from Au35Ag65 alloy films with about
100 nm thickness. The average pore diameter was 10–40
nm, according to the dealloying temperature and time.
RESULTS: Figure 1 shows broadband reflectivity
spectra of NPG with various average pore sizes. The horizontal axis is in a logarithm to show the wide spectral
range. Fine structures in IR spectra are due to CO2 andH2O in atmosphere. Measurement of the lack region at
terahertz wave is under way at the UVSOR facility. Peaks
at 0.06eV are due to reflection of the substrate quartz. It
is especially strong at 42nm pore sample because of void
content (low average density) of the large porous thinfilm. Small structures at infrared region are due to absorption by CO2 and H2O in atmosphere. Peaks at
1.45eV are due to reflectivity dip of the reference Al
mirror. Plasmonic characteristic spectral changes wereobserved from IR to UV region. They depend on the pore
size.

10-

10-1
PHOTON ENERGY(eV)

100

Fig. 2. Drude curve fitting of the energy loss function
spectra of NPG membranes on quartz substrates.
Dashed lines show fitting curves for each pore size
sample.
Plasmon fitting by classical Drude model in energy loss
function spectra is shown in Fig. 2. Energy loss function,Im(1/ε), is proportional to absorption intensity by transverse wave. Systematic decrease of the plasma frequency
with pore size increment was observed. Plasma frequencyof bulk gold is 8.6eV, therefore, these ω p for pore samples
are much small. The promoter effect seems to be relatedwith small values of these parameters. The origin of poresize dependence of the promoter effect is still not clear.
REFERENCE:[1] Bierner, J. et al., Nature Materials, 8 (2009) 47-51.

採択課題番号 24021 超イオン導電体におけるコヒーレントミリ波誘起イオン伝導の検証 共同通常
（東北学院大・工）淡野照義（京大・原子炉）高橋俊晴

CO4-5Tritium Release from Li4SiO4 Ceramic Breeder Materials Doped with Ti

K. Munakata, K. Wada and T. Takeishi1
Department Faculty of Engineering and Resource Science, Akita University
1
Graduate School of Engineering Science, Kyushu University
INTRODUCTION: The effect of titanium on the tritium
release from Li4SiO4 ceramic breeder material was investigated. Titanium was doped in Li4SiO4 during the fabrication process so-called melt-spraying method. Tritium
release curves were obtained in a series of experiments
carried out using the out-of-pile temperature programmed desorption (TPD) technique. Tritium release
curves obtained for solid breeders with different titanium
composition were compared to examine the effect of catalyst metal on tritium release.
EXPERIMENTS: The titanium-doped Li4SiO4 ceramic
breeder materials were prepared and donated by Karlsruhe Institute of Technology (KIT). These ceramic
breeders with catalytic metals encapsulated in a quartz
tube were irradiated in Kyoto University Research Reactor (KUR) in the thermal neutron with the flux of 5.
5×1012 cm-2s-1 in the He atmosphere.
Release curves of bred tritium from the breeder pebbles were obtained using the out-pile temperature programmed desorption techniques. The experimental apparatus is schematically shown by Figure 1. The volumes ofionization chambers are 66 cc and the time constant for
replacement of the gas inside the chambers [volume] /[flow rate] is 40 seconds. The first ionization chamber
was used to measure the total tritium concentration andthe second chamber placed after a water bubbler wasused to measure that of molecular form tritium in thepurge gas, respectively.
Water vapor was introduced to the purge gas at the inlet of the ionization chamber when dry nitrogen gas or
nitrogen with hydrogen gas was used as the purge gas tominimize the tritium memory effect according to the result obtained in the previous works.
RESULTS: Figure 2 shows comparison of experimental tritium release curves for the Li4SiO4 samples
irradiated for 30 minutes with neutron flux with 5. 5×1012
cm-2s-1 [1/cm2s]. The sweep gases of 1,000 ppm H2/Ar
gas were used in the experiments. Comparison of Figs.
2(a) and (b) indicates that tritium is released at lower

採択課題番号

24026

relatively temperatures when titanium was doped to the
Li4SiO4 breeder material. However, ionization chamber 2
was not worked. Therefore, a re-experiment needs to be
conducted.

CuO
Sample Bed
Cold Trap(Molecular sieve-5A)

Volumes of ionizationchambers are 66cm3 each other.

10000ppm
H2/N2Gas
1000ppmH2/N2gas
or dry N2 gas

I.C.2

I.C.1

BBuubbbblleerrFig.1. Schematic diagram of experimental
apparatus(a)Temperature

HT + HTO(b)
Temperature

HT + HTO

Fig. 2. Tritium release curves(a) Li4SiO4 ceramic breeder material(b) Li4SiO4 ceramic breeder material
doped with titanium

核融合炉トリチウム増殖材料および中性子増倍材料からのトリチウムの放出挙動の解明（秋田大･工学資源）宗像健三、和田孝平 （九大･工学研究員）竹石敏治

一般通常

CO4-6

Absorption Spectroscopy with the Coherent THz Radiationfrom Linac Electron Beams

S. Okuda, T. Kojima, S. Shimomura and T. Takahashi1
Radiation Research Center, Osaka Prefecture University
Research Reactor Institute, Kyoto University

1

INTRODUCTION: The coherent synchrotron andtransition radiation (CSR, CTR) from electron bunches ofa linear accelerator (linac) have continuous spectra in a
submillimeter to millimeter wavelength range at extremely high peak-intensities. The coherent radiation(CR) light sources developed were applied to absorption
spectroscopy [1-4] especially for matters with relatively
strong light absorbance.
The absorption spectroscopy system using the CTR
from the electron beams of the 45 MeV L-band electron
linac was established at KURRI [5]. The CR has
high-intensity pulsed electric field and possibly excites
matters in a short period. The experimental configurations have been modified for investigating such effects.
In the present work the slight changes of the transmission spectra have been observed for various kinds ofmatters. In order to investigate the phenomena a new
pump-probe system has been developed in Osaka Prefecture University (OPU).
CHARACTERISTICS OF THE CR: The CSR isemitted as a pulsed and linearly polarized unipolar electric field. The light can produce the intense pulsed electric field and would cause the excitation in a matter. In
the case of an electron linac the electric field is expected
to be about 50 MV/cm. The pulse shape of the electric
filed is determined by the electron bunch shape.
EXPERIMENTAL METHOD: The new experimental
configurations modified for the absorption spectroscopy
investigating the light intensity effects are schematicallyshown in Fig. 1. The output light from a light sourcechamber was focused at a light collimator 8 mmφ in diameter. The spectrum of light after passing through thesample was measured with a Martin-Puplett type interferometer and a liquid-He-cooled silicon bolometer. In
the previous experimental configurations the sample was
located on the light path between the interferometer andthe detector [5].

The spectrum was sufficiently stable during the measurements within ±2-3% in a wavenumber range of 4-12
cm-1. The wavenumber resolution was 0.2 cm-1. The details of the measurements are described in ref. 3.
RESULTS AND DISCUSSION: The wavenumber
dependence of the transmittance of light was measured
for various kinds of matters under the experimental configurations shown in Fig. 1. The change of the transmittance was observed by changing the light intensity [6].
These results seem to suggest some change in the sample
induced by the pulsed CTR.
Coherent radiation
Electron linac

Radiator

SamplePulsed electrons

Monochromator

Detector

Oscilloscope

Fig. 2. Schematic diagram of the pump-probe experimental setup.
The new system for the pump-probe experiments byusing the 16 MeV S-band linac in OPU has been developed [7]. Figure 2 shows schematically the componentsof the system, where the samples are excited with theelectron beams or the pulsed CR in a short period. The
CSR and the CTR is used as light sources. This will beapplied to investigating the transient phenomena inducedby the pulsed CR or electron beams by using CR asprobe.
The light sources developed by using the electron
linacs in KURRI and OPU will be applied to the excitation of matters and to the pump-probe experiments.
REFERENCES:[1] T. Takahashi et al., Rev. Sci. Instrum. 69 (1998) 3770.
[2] K. Yokoyama, Y. Miyauchi, S. Okuda, R. Kato and T.
Takahashi, Proc. 20th Int. Free-Electron Laser Conf.
(1998, Williamsburg, USA) II 17-18.
[3] S. Okuda, M. Nakamura, K. Yokoyama, R. Kato and
T. Takahashi, Nucl. Instrum. Meth. A445 (2000) 267.
[4] S. Okuda et al., Radiat. Phys. Chem. 75 (2006) 903.
[5] S. Okuda and T. Takahashi, Infrared Phys. Technol.
51 (2008) 410.
[6] S. Okuda and T. Takahashi, Proc. 35th Int. Conf. on
Infrared, Millimeter and Terahertz Waves (2010, Rome,
Italy), IEEE Xplore 10.1109/ICIMW.2010.5612474.
[7] S. Okuda, T. Kojima, R. Taniguchi, Proc. XXV Linear
Accelerator Conf. (2010, Tsukuba, Japan) 79-81.

Fig. 1. Schematic diagram showing the new configurations for absorption spectroscopy using the CTR.

採択課題番号24056ライナック電子線からのコヒーレントテラヘルツ放射による吸収分光 共同通常
（阪府大・地域連携）奥田修一、小嶋崇夫、下邨広元 （京大・原子炉）高橋俊晴

-Ray-Induced Preparation of Porous Binary Polymer Hydrogels

N. Sato, Y. Oba, M. Sugiyama, A. Nakamura1 and
N. Hiramatsu1
Research Reactor Institute, Kyoto University
1
Faculty of Science, Fukuoka University

INTRODUCTION: Polymer gels, which are composed of crosslinked polymer chains, have network
structure that provides various unique properties different
from polymer solutions or polymer solids. One of themis swelling property. Polymer gels can contain large
amount of liquids, especially water, inside while keeping
its structure. Under favor of this property, polymer gels
are widely used as a commodity material in the humanlife.
Polymer gels also attract scientific interests. There
are many factors that characterize the structure of polymer gels: crosslink density, chemical property of component chains, electrical charge, and crosslink inhomogeneity. To obtain high quality materials using polymer gels,
it is essential to reveal the relationship between structure
and physical properties.
Polymer gels can be prepared through -ray irradiation,
as well as the chemical crosslinking method. rays cangenerate reactive species directly in the irradiated materials, and thereby start the reaction without chemical additives such as reaction initiators, crosslinkers or catalysts.
This advantage leads to the merit of reducing the chemical impurities in the final products, which is favorable forbio-compatible materials. In addition, less structural
inhomogeneity of radiation-prepared gels than chemically-prepared gels is also advantageous for high-quality
polymer gels.
The -ray-induced gel preparation method is also applicable to fabricate multi-component gels. Additional
components can be introduced into preformed gels andfirmly bonded onto existing polymer networks by radiation reaction.
In this study, we prepared two-component polymerhydrogels by the -ray-induced gel preparation method.
Poly(ethylene glycol) (PEG) is employed as a matrix gel
and poly(N-isopropylacrylamide) (PNIPAm) is introduced as a second component. PNIPAm is well known
for its thermoresponsive property: swollen PNIPAm hydrogels rapidly shrink at around 34 °C when heated. By
incorporation PNIPAm into PEG hydrogels, it can be
expected that common PEG hydrogel shows such thermoresponsive behavior. Furthermore, binary porous
gels can be made by -irradiation. Difference in structure and physical property between nonporous and porous
gels was also revealed in this study.
The structural feature of nonporous and porous gelscan be analyzed by several methods. Small-angle X-ray
and neutron scattering analysis is useful for nm-order
structure, which is discussed in another report. In thisstudy, we are under investigating the structural differenceby thermal analysis like differential scanning calorimetry.
In this report, however, gel preparation and thermoresponsive behavior of these gels are described.
EXPERIMENTS: Typical preparation procedure is asfollows. 10 wt% of PEG aqueous solution was sealed ina vial after removing oxygen by nitrogen bubbling. It
was then irradiated with rays for 60 kGy at a dose rateof 1.0 kGy/h. After irradiation, the product gels were
purified by removing unreacted PEG by rinsing with water several times. These PEG gels were completely
dried, and then immersed in a deoxygenated 10 wt%
NIPAm
monomeraqueoussolution.
The
NIPAm-impregnant gels were irradiated with  rays again
for 3.0 kGy at a dose rate of 1.0 kGy/h. After irradiation, unreacted monomers were removed by rinsing withwater, and thus obtained final product gels. As for porous gels, silica microparticles (200 nm and 1000 nm)
were ultrasonically dispersed in a PEG solution before
irradiation and removed by hydrofluoric acid treatment
after irradiation.
RESULTS AND DISCUSSION:A PEG/PNIPAm
hydrogel shows no difference in appearance from pure
PEG gels at temperatures lower than the transition temperature around 34 °C. When heated, however, the binary gel shrinks at around 34°C and becomes white andopaque, similarly to the PNIPAm gels. The shrunk gel
is still soft and elastic although its size reduces greatly,
which differs from pure PNIPAm gels. The porous gel
is not dissimilar from the nonporous gel in appearance,
but the change in the swelling ratio (weight ratio of thegel in the swollen state to the dried state) of the porous
gel with increasing temperature is smaller than that of the
nonporous gels, which means the porous gels are lessshrinkable (Fig. 1). This is due to the PNIPAm chainsare localized in the pore space of the PEG matrix gel.
Only localized PNIAPm chains preferentially shrink in
the pore, which makes the whole gel less shrinkable.

30

Swelling ratio

CO4-7

20

10

0

1
2
3
PNIPAm content
Fig. 1. Swelling behavior of porous and nonporous(open and solid symbols). Porous gels show smaller
size change.

採択課題番号 24059 放射線誘起合成した多成分系高分子ゲルの熱的挙動と構造解析（京大・原子炉）佐藤 信浩、杉山 正明（福岡大・理）平松 信康、中村 忠嗣

共同通常

CO4-8γ-Ray Irradiation Effects for Metal Complexes
with Cage-Type Silsesquioxane Ligand

Y. Okaue, T. Yokoyama, H. Ohashi1 and F. Yoshimura
Department of Chemistry, Faculty of Sciences, Kyushu
University
1
Faculty of Arts and Science, Kyushu University
INTRODUCTION: Upon 60Co γ-ray irradiation on
Q8M8 ([(CH3)3SiO]8(SiO1.5)8) with double four-ring(D4R) cage structure as shown in Fig. 1, hydrogen atom
is stably encapsulated in D4R cage at room temperature.
Encapsulation of hydrogen atom can be confirmed by
ESR spectroscopy. Hydrogen atom encapsulated in
D4R cage of silsesquioxane interacts magnetically withparamagnetic oxygen molecules outside D4R cage tochange ESR signal intensity and saturation behavior.[1]The purpose of this study is the research for interactions
between paramagnetic metal ion and encapsulated hydrogen atom in a single molecule by introducing coordination sites for metal ion to silsesquioxane with D4R
cage structure. In this experiment, Schiff base site wasadopted as the coordination site to form stable complexes
with many metal ions easily.
R1
R2
O
O Si
O Si
R1
O
Si
Si R1
O
O
O
O
Si
R
Si O
R1
Si O
Si O
O
R1
R1

Fig. 1.

Q8M8 ; R1, R2 = OSi(CH3)3
T8iBu7Ap ; R1 = CH2CH(CH3)2R2 = CH2CH2CH2NH2

Table 1.
Metal
Mn(II)
Co(II)
Ni(II)Cu(II)
Zn(II)

Colors and yields for M(L1)2
Color
Yield / %brown
70
light yellow
21
light green
79
dark green
77
yellowish white54

ESR spectra of all metal(II) complexes showed the characteristic two hyperfine lines separated with about 50 mT
due to hydrogen atom nucleus (I=1/2). As an example,
ESR spectrum of the irradiated Ni(L1)2 was shown in Fig.
2. It was concluded that all metal(II) complexes could
encapsulate hydrogen atom in the D4R cage of silsesquioxane unit. On the other hand, in the case of ESR spectrum of the irradiated Mn(L1)2, the broad signal around
336 mT due to Mn(II) species was confirmed in addition
to the characteristic two lines due to hydrogen atom asshown in Fig. 3.
Magnetic interactions between metal ion and encapsulated hydrogen atom in a single molecule for each complex
will be examined.
REFERENCE:[1] R. Sasamori, Y. Okaue, T. Isobe and Y. Matsuda,
Science, 265 (1994) 1691-1694.

L1 ; R1 = CH2CH(CH3)2
R2 =

N
HO

D4R cage structure of silsesquioxane.

EXPERIMENTS: Ligand L1 with D4R cage structure
was prepared by the reaction between T8iBu7Ap and salicylaldehyde. Various metal(II) complexes were synthesized as follows: Metal(II) acetate and L1 were stirredin methanol at 60 °C for 2-6 h. The resulting solution
was concentrated under reduced pressure and cooled toroom temperature. Characterizations were made by IR
spectroscopy, 1H NMR spectroscopy, and elemental
analyses. Powder samples of metal(II) complexes were
irradiated with γ-ray under air at room temperature in60
Co γ-Ray Irradiation Facility at Kyoto University Research Reactor Institute. Irradiated samples were recrystallized from hexane. X-band ESR spectra for therecrystallized powder samples were measured on JEOLJES-FA200 spectrometer under air at room temperature.

Fig. 2.

RESULTS: Ligand L1 was obtained as yellow powder.
The maximum yield was ca. 40%. Metal(II) complexes
for Mn(II), Co(II), Ni(II), Cu(II), and Zn(II) were isolatedas M(L1)2. The colors and yields of the metal(II) complexes were listed in Table 1.

236

286

336

386

Magnetic Field / mT
ESR spectrum of irradiated Ni(L1)2.

336

436

Magnetic Field / mT
Fig. 3.

ESR spectrum of irradiated Mn(L1)2.

採択課題番号 24060	
  かご型シルセスキオキサン配位子を用いた金属錯体への	
 
一般通常	
 
ガンマ線照射効果	 （九大院・理）岡上吉広、横山拓史（九大・基幹教育院）大橋弘範（九大・理）吉村富治郎	
 Synthesis of Metal Nanoparticles Under the Gamma-ray Irradiation Field

F. Hori, K. Nagata, T. Hori, A. Okamoto, A. Iwase and
M. Sakamoto1
Dept. of Mater. Sci., Osaka Prefecture University
1
Research Reactor Institute, Kyoto University

INTRODUCTION: It is known that metallic
nanoparticles have some specific properties, which are
not appear in bulk materials such as catalytic activities,
magnetic properties and so on. Also the character of them
depends on its size, shape, structure, chemicalcomposition and so on. For instance, it is known that Au
nanoparticles exhibit the surface plasmon resonances(SPRs) in specific wavelength at about 520 nm. They
have many possibilities to applied for various industrial
fields. Generally, many kinds of metal nanoparticles
commercially are synthesized by using chemical reaction
method. On the other hands, it has been reported thatspecific feature of metallic nanoparticles can besynthesized under energetic irradiation fields, such as
ultrasonic, electron, gamma-ray, plasma and so on [1-3].
Using these irradiation reduction methods, it is possible
to fabricate the unexpected structured nanoparticles like acore-shell type A-B that is not appears in phase diagram[3]. In this study, we have tried to fabricate Cu
nanoparticles, which is not easy to reduce in aqueous
solution by chemical reaction, using gamma-ray
irradiation reduction method.

EXPERIMENTS: Aqueous solutions with a given
concentration of copper complex ((CH3COO)2Cu·H2O)
with an additive of of sodium dodecyl sulfate (SDS) anda radical scavenger of diethylene glycol (DEG). The
solution was argon purged and sealed into polystyrene
vessels. They were irradiated at about 300 K with 1.17
and 1.33 MeV gamma-rays from 60Co radio active sourceat gamma irradiation facility in KURRI, Kyoto
University. The total dose was fixed to 23.4 kGy withdose rate of 15.6 kGy/h. UV–vis absorption spectra were
measuredby
using
Shimadzu
UV-2550
spectrophotometer in the wavelength range in 300-800
nm and the shapes and the structures for all colloidal
products were observed by conventional TEM (JEOL
JEM-200CX). Samples for TEM observations were madeby putting a drop of colloidal solutions on a carbon filmwith a Mo mesh and dried them in a vacuum.

RESULTS:
Figure 1 shows the UV/vis absorption spectra for
aqueous solutions before and after gamma-ray irradiation.
There is no absorption peak in aqueous solution
including Cu ions before irradiation. It appears two
absorption peaks around 300 and 570 nm after
gamma-ray irradiation. The peak around 570 nm
corresponds to the surface plasmon resonance from pureCu nanoparticles [4]. The broadened peak around300-400 nm may originates from the absorption of oxidic
copper nanoparticles, such as CuO and Cu2O. Therefore,both pure Cu and oxidic-Cu nanoparticles were generated
in this solution by gamma-ray irradiation. TEM
observation shows that generated particles by gamma-ray
irradiation are monodispersive spherical shape and its
average diameter is the orders of 10 nm. As a conclude
that Cu nanoparticles were successfully synthesizedunder the gamma-ray irradiation field.

1
Cu0.5mM-SDS10mM	
 15.6kGy/h	
 23.4kGy

absorption intensity (arb.u.)

CO4-9

0.8

before irradiation
after irradiation

0.6
0.4
0.2
0
200

300

400 500 600
wavelength (nm)

700

800

Fig. 1 UV/vis absorption spectra of aqueous solutions
including Cu-ions before and after gamma-ray
irradiation.

REFERENCES:[1] T.Akita et al., Catalysis Today 131 (2008) 90-97.
[2] M.Nakanishi et al., Appl. Surf. Sci. 241 (2005)	
  209-212.
[3] N.Taguchi et al., Radiation Phys. and Chem. 78 (2009)
1049-1053.
[4] Szu-Han Wu et al., J. of Colloid and Interface Sci. Chem.
273 (2004) 165-169.

採択課題番号 2463	  	  ガンマ線照射還元を利用した貴金属ナノ微粒子の創成（阪府大・工）堀史説、永田光一郎、堀達朗、岡本晃彦、岩瀬彰宏	
 	
 (京大・原子炉)坂本雅昭	
 共同通常 

Magnetic Order of Fe in Normal Conducting Sr2VFeAsO3-d
Probed by 57Fe Mössbauer Spectroscopy

INTRODUCTION: The discovery of high-temperature
superconductivity in layered ion-based mixed anion
compounds [1,2,3] represents an important breakthroughin the field of condensed matter physics. Since the discovery of the compounds, much attention has been paid
to searching for new superconductors with higher superconducting transition temperature (Tc) in this family. In
this study, a polycrystalline sample of Sr2VFeAsO3-d as
nominally d = 0.52 was prepared. The sample included
minor impurity phases. The sample does not exhibit bulk
superconductivity, and exhibits finite spontaneous magnetization and AF order of Fe in the sublattice at T < 15
K. These results support to obtain electronic and magnetic state phase diagram of Sr2VFeAsO3-d.
EXPERIMENTS: Polycrystalline samples were prepared by the solid-state reactions in a sealed silica tube
using dehydrated SrO, FeAs, V2O5, V as starting materials, reported previously. [4] The dehydrated SrO was
prepared by heating commercial Sr(OH)28H2O powder(Sigma Aldrich Japan Co. Ltd; 99.995 wt.%) at 900 C
for 10 h in air. To obtain FeAs powder, Fe (Ko-jundo
Chemical Laboratory; 99.99 wt.%) and As (Ko-jundo
Chemical Laboratory; 99.9999 wt.%) were mixed in a
stoichiometric ratio of 1 : 1 and heated at 600 C for 10 hin an evacuated silica tube. Then they were mixed withdehydrated SrO, V2O5 (Sigma Aldrich Japan Co. Ltd;99.99 wt.%) and V (Sigma Aldrich Japan Co. Ltd; 99.9wt.%) in the formula Sr2VFeAsO3-d as nominally d= 0.
The powder was pressed into the pellet shape. The pellet
was loaded in an alumina tube, preventing possible reactions with the quartz tube. The alumina tube, placed in asealed silica tube was heated to 1300 C at a rate of 30
K/h, kept for 20 h and cooled down to room temperature.
Then, the surface of the sample was polished by abrasive
paper sheet made of SiC (Sankyo Rikagaku Co. Ltd; Gritno. 400 and 1000). To prevent the silica tube from collapsing during the reaction, the silica tube was filled withhigh purity Ar gas with a pressure of 0.2 atm at room
temperature (RT). All procedures were carried out in an
Ar-filled glove box (MIWA Mfg; O2, H2O < 1 ppm). The
crystal structure, phase purity, and lattice constants of theresulting powders were examined by powder X-ray diffraction (XRD; Rigaku RINT2500 Ultra18) with CuKradiation. DC electrical resistivity was measured by afour-probe technique using gold electrodes (Nilaco; purity 99.95 wt.%) at temperatures of 5 K to 300 K. 57Fe

equipment at temperatures = 4.2-300 K.
RESULTS: Our results are summarized as follows: (i)Stoichiometric Sr2VFeAsO3 sample was not synthesized
as a single phase indicating that finite oxygen deficiency
is inevitable for the compound. The sample has rather
large c axis than other reports. This result suggests that
normal conductivity of this compound appears when thec axis is rather large. (ii) As shown in Fig. 1, the magnetic
state of normal conducting sample exhibits the AF stateof Fe at T < 15 K. We concluded that superconductivity
does not coexist with magnetic ordered Fe sublattice. (iii)
Although purer samples are required for determining theoxygen contents of Sr2VFeAsO3-d, our results should help
in making the electronic and magnetic phase diagram of
Sr2VFeAsO3-d.
1.00

Transmission

Department of Applied Physics and Physico-Informatics,
Keio University
1
Research Reactor Institute, Kyoto University

Mössbauer spectra were obtained using conventional

15K

0.98

0.96

1.00

Transmission

Y. Tojo, T. Nakamura, M. Matoba, S. Kitao1, M. Seto1
and Y. Kamihara

10K

0.99
0.98

1.00

Transmission

CO4-10

4.2K

0.99

0.98

0.97

Sr2VFeAsO3-dd=0.52
-4

-2

0

2

4

Velocity (mm/s)

Fig. 1. 57Fe Mössbauer spectra of polycrystalline
Sr2VFeAsO3-d at several temperatures described in
the figure.
REFERENCES:[1] Y. Kamihara, et al., J. Am. Chem. Soc., 130 (2008)
3296.
[2] Y. Kamihara, Hyperfine Interact., 208 (2012) 123.
[3] X. Zhu, et al., Phys. Rev. B 79 (2009) 220512.
[4] Y. Tojo, et al., J. Appl. Phys., 113 (2013) 17E157.

採択課題番号 24064
メスバウア分光法による重い電子系の解析（京大・原子炉）瀬戸誠、北尾真司（慶應義塾大・理工）神原陽一、中村哲朗

共同通常CO4-11

Complex Structure of Ions Coordinated with Hydrophilic Polymer. 13:

A. Kawaguchi , Y. Gotoh1 and Y. Morimoto
KURRI
Facuty of Text. Sci. and Tech., Shinshu Univ.

1

INTRODUCTION:
We have reported composite
structure brought by in situ preparation through"secondary doping" by diffusion of metallic ions into
iodine-doped hydrophilic polymers. Polyiodide ions, In( n = 3, 5,,), which have been doped into the polymers
previously, enhances following diffusion of othermolecules or ions into matrix polymer at room
temperature.[1,2] As one of easier cases for diffusing
operation of metallic ion, we have achieved spontaneous
diffusion of silver ion (Ag+) from AgNO3(aq) into
"iodine-doped polyamide-6 (PA6, NylonTM-6)". This
process can develop precipitation of silver iodide (AgI) as
inorganic salt at inner space of polymeric matrix andconsequently provides hybrid composite for unlimited
shape or size without plasticizing matrix.[3-5]And, considering high affinity between polyiodide ionsand other hydrophilic polymers (for example, PVA,
starch,,), such injection procedures of inorganic ions canbe applied widely for various materials; processing forhybridization can be achieved a posteriori for polymericmaterials after their forming or structuring, so the process
for hybrid composite can be applied as matrix for fiber,
films, oriented structures, biological structures, textiles,
micro beads and more products with arbitrary shapes andsize.[5] As a case of such wide application, doping
process with polyiodide was preliminarily applied forfoam structure of polyurethane (PU).
EXPERIMENTS: Several kinds of commercial products"Kurara-foam"TM (provided by Kurabo co.ltd.) were used
as non-doped PU matrixes; all samples are softurethane-form and are made from (poly)ester as soft
segments. (In following preliminary experiments, detailsof the samples or their accurate components were notpresented by the provider.) Pieces of PU foams were
immersed into KI-I2(aq)/0.4N. (iodine-doping) Next,
these iodine-doped PU forms were immersed into
Some
AgNO3(aq)/1M. (secondary doping of Ag+)
samples were observed with scanning electron
microscopy (SEM) or wide-angle X-ray diffraction(WAXD).
RESULTS AND DISCUSSION: Generally, PU ispolymer composed with two components: hard segment
or
harddomaincontaining
urethanegroup(-NH-CO-NH-) and soft segments or soft domaincomposed by polyester ( or polyether ) binding the hard
segments.
PU shows low crystallinity and often
amorphous induced by flexible segments.[6] On theother hand, considering polarization given by the urethanegroup, effects on interaction with polyiodide ions in hard
segment can be expected for similarity as polyamide (PA),which often indicates ordered structures by intercalationor phase transition induced by polyiodide ions orvariation in following hybrid composite.[7] Even if PU
is generally amorphous, hybridization of porous foamshould introduce some novel functionalities since general
hybrid composites can be hardly formed as porous
structure.
Consequently, iodine-doping to PU foam samples could
be achieved easily at R.T. However, while diffusion ofiodine advanced spontaneously from KI-I2(aq), release(volatilization) of iodine was also activated from theiodine-doped PU and translation of polyiodide should bealso in the polymer. Then, contents or components ofpolyiodide ion were fluctuated widely and effective data
were not got for quantitative discussion at present.
Generally speaking, under plenty of diffusion and releaseof iodine, some tendency was observed as softening thePU matrix induced by iodine-doping.
Therefore, it may be too early to estimate results
quantitatively after "secondary doping" of Ag+ ion in PU
matrixes. However, macroscopic character of eachsample was widely modified as hybrid composite through"secondary doping". For example, while all original PU
foams had been soft and flexible and elastic porous
materials, hibrid composites given by inner-precipitationof AgI were changed in quality; some of them werechanged too brittle to be stretched or others were soft but
sticky. It is assumed that such variation is originated incomplication of coordination of iodine with PU;
polyiodide can be interacted not only with explicit
polarized groups (such as urethane group in hard domain)
but soft segment chain (such as polyester) between them.
And larger proportion of the latter soft segment chain may
result the experimental uncertainty or instability in the PU
hybridization.

Fig. Composite with PU matrix after "secondary doping" with Ag+;
porous foam structure was modified into hybrid composite byprecipitated AgI filler.

ACKNOWLEDGEMENTS: PU samples were provided
by Kurabo co.ltd., The authors express great thanks forthe cooperative researchers.
REFERENCES:[1] A. Kawaguchi, Sens. Actuators B, 73 (2001) 174-178.
[2] Y. Gotoh, et.al., Polym. Prep. Jpn., 51 (2002), 2259-2259.
[3] A. Kawaguchi, et.al., ibid., 53 (2004), 3372-3372.
[4] A. Kawaguchi, et.al., ibid., 56 (2007), 5471-5472.
[5] patent applied.
[6] "Fundamentals and Applications in Polyurethanes." (in Japanese), Ed.
K. Matsunaga, (2006, CMC Press., Tokyo).
[7] A. Kawaguchi, et.al., Polym. Prep. Jpn., 53 (2004), 3737-3738.

採択課題番号24079
親水性高分子−金属塩ナノコンポジットの調製と構造（京大・原子炉）川口昭夫、森本幸生（信州大・繊維）後藤康夫

共同通常

Design and Preparation of the Electrochemical Cell for the Study of theIon Distribution at the Electrochemical Interfaces ofIonic Liquids Using Neutron Reflectometry

N. Nishi, J. Uchiyashiki and M. Hino1
Graduate School of Engineering, Kyoto University
1
Research Reactor Institute, Kyoto University
INTRODUCTION: Ionic liquids (ILs), which are liquid salts entirely composed of cations and anions, havepotential applications to electrochemical devices becauseof their several characteristics such as negligible volatility and wide potential window at the IL/electrode interface. The knowledge of the molecular-level structure at
IL/electrode interface is important to optimize the performance of the IL electrochemical devices. Theoreticalstudies have revealed several unique features of the distribution of ions at IL/electrode interface, such as
overscreening effect and lattice-saturation effect [1],while experimental studies that shed light on such features are limited to a few. In this study, we aimed toinvestigate the distribution of ions at the IL/electrodeinterface using neutron reflectometry. In this report, we
will show the results of the design and the preparation ofelectrode film, which is crucial to sensitively detect theion distribution.
EXPERIMENTS: Thin-layer Al4Ti electrode film was
prepared on a silicon wafer using a sputter apparatus.
For IL, trioctylmethylammonium bis(nonafluorobutanesulfonyl)amide ([TOMA+] [C4C4N−]) was prepared fromthe hydrophilic salts of the IL-constituent ions([TOMA+]Cl− and Li+[C4C4N−]) and purified using column chromatography. Cyclic voltammograms at the[TOMA+][C4C4N−]/film interface were recorded for thetwo-electrode electrochemical cell.

(a)

(b)

Fig. 1. (a) Side view and (b) top view of the electrochemical cell for neutron reflectivity measurements.
RESULTS: Figure 1 shows the electrochemical cell
designed and prepared for neutron reflectometry. IL,[TOMA+][C4C4N−], was sandwiched with two Al4Ti
electrode films that were sputtered on the surface of silicon wafers. The surface of one of the silicon wafers
was polished and the surface roughness evaluated using
x-ray reflectometry was ~3 Å. The interface between[TOMA+][C4C4N−] and the Al4Ti electrode film on this

採択課題番号 24082

polished silicon surface will be “target” interface in neutron reflectometry. The surface of the other silicon wafer was non-polished because we do not want to see reflected beam from this surface and thus want to minimize
and neglect the reflectivity from this surface. To prevent short circuit of the cell due to unintended contact of
the two electrodes, thin layer glass sheet with a thicknessof 50 m was inserted as a spacer between the two electrodes. The area of the electrode was 3050 mm2 inorder to keep the sufficient area to cover a long footprintof neutron beam with a grazing incident angle.

10

I / A

CO4-12

0

-10
-1

0
E / mV

1

Fig. 2. Cyclic voltammogram for the electrochemical cell shown in Fig.1. Scan rate: 0.1 V s−1; electrode surface area: 15 cm2; ionic liquid layer spacing: 50 m.
We tested the electrochemical polarizability of the[TOMA+][C4C4N−]/electrode interface using cyclic
voltammetry. Figure 2 shows the cyclic voltammogramwith a scan rate of 0.1 V s−1. One can see electrochemical window with a width of 1.6 V available for the cell.
The capacitance of the [TOMA+][C4C4N−]/electrode interface was estimated from the capacitive current recorded in the cyclic voltammogram. The capacitance was−2−2
evaluated to be 3 F cm , lower than ~10 F cm , areported value for the interface between metal and another kind of IL with smaller ions [1]. This lowering ispresumably due to larger ions for [TOMA+][C4C4N−]
than those for the IL in ref. 1 or oxide layer formed at thesurface of the Al4Ti film.
REFERENCES:[1] B. Roling, M. Drüschler, B. Huber, Faraday Discuss.,
154 (2012) 303.

イオン液体｜固体界面におけるイオン多層構造の中性子反射率測定による研究（京大院・工）西 直哉、内屋敷純也（京大・原子炉）日野正裕

共同通常Irradiation Effect on Tritum Migration Processin Tritium Breeding Material for Fusion Reactor

INTRODUCTION: Many studies have been carriedout to establish a tritium recovery system in fusion reactors. Especially, many researchers focus on lithium titanate (Li2TiO3) because it is one of the candidates as thetritium breeding material for ITER due to its good tritium
recovery efficiency and chemical stability. It is necessary
to clarify tritium behavior from the viewpoint of fuel cycle in neutron-irradiated Li2TiO3. Recently, the use of
Li2+xTiO3 (x=0.2, 0.4), which is the lithium-enriched
Li2TiO3, is proposed to improve the tritium breeding ratio.
Hara et al., reported that both of Li2.2TiO3 and Li2.4TiO3
were the mixture of Li2TiO3 and Li4TiO4, indicating that
excess lithium induced the formation of Li4TiO4 structure
in Li2TiO3 structure during fabrication [1]. In this study,
tritium was generated in Li4TiO4 by thermal neutron irradiation or introduced by thermal tritium gas absorption.
tritium release behavior for Li4TiO4 was studied bymeans of Thermal Desorption Spectroscopy (TDS). The
tritium release kinetics for Li2+xTiO3 with thermal neutron irradiation were also evaluated for comparison.
EXPERIMENTAL: Powders of Li4TiO4 and Li2+xTiO3
purchased from Kaken Co. were used as samples. These
were irradiated by thermal neutron with the fluence of
3.3 x 1015 n cm-2 at the Kyoto University Research Reactor Institute (KURRI). Out-of-pile tritium release experiments were performed in tritium-TDS system at Shizuoka University. In TDS experiments, the samples were
heated up to 1273 K. FT-IR (Fourier Transform Infrared
Spectroscopy) measurements were also carried out for
Li4TiO4 exposed to pure D2 gas to reveal chemical statesof deuterium in Li4TiO4. Changes of crystal structure of
Li4TiO4 by D2 gas exposure were also investigated by
X-ray diffraction technique at Toyama University.
RESULTS: Tritium-TDS spectrum with the heating
rate of 5 K min-1 for Li2+xTiO3 with thermal neutron irradiation were consisted of two release stages at 480 K and
580 K, namely Peak 1 and 2, respectively. The activationenergy of Peak 1 was estimated to be around 0.37 eV,
although that of Peak 2, about 0.63 eV, corresponding to-1

Radioscience Research Laboratory, Faculty of Science,
Shizuoka University
1
Research Reactor Institute, Kyoto University

the activation energy of tritium diffusion in Li2TiO3[2].
Fig. 1 shows the tritium-TDS spectrum for Li4TiO4 withthermal neutron irradiation measured under the heating
rate of 0.5 K min-1. Two tritium release stages named as
Peaks A and B were observed at 450 K and 600 K, respectively. As the release temperature regions of Peak 1
and Peak A were almost the same, tritium releases ofthese peaks were considered to be originated from thesame process. In addition, it was found that O-D bonds
were formed in Li4TiO4 by D2 gas exposure by FT-IR
measurements. On the other hand, diffraction patterns of
Li4TiO4 with D2 gas exposure were quite similar to thatwithout D2 gas exposure, indicating that LiOD structure(crystal) was not formed in Li4TiO4. It was reported that
Li4TiO4 is reactive with water vapor and forms O-H
bonds on the surface[1], considering that water vapor as
impurity was adsorbed on the surface of Li 4TiO4 during
air exposure or TDS measurements, which would induce
the formation of O-H bonds. Therefore, overall tritium
release for Li4TiO4 was governed by decomposition of
O-T bonds and appeared as Peak B in TDS spectra.

-1

K. Okuno, Y. Oya, M. Kobayashi, K. Kawasaki
T. Fujishima, Y. Miyahara, H. Uchimura, T. Taguchi
K. Toda, R. Miura, T. Fujii1, and H. Yamana1

Tritium release rate / Bq s g

CO4-1330

Peak A

20

Peak B

10
0
300

400

500 600 700
Temperature / K

800

900

Fig. 1. Tritium-TDS spectrum of Li4TiO4with thermal neutron irradiation

REFERENCES:[1] M. Hara et al., J. Nucl. Mater. 404 (2010) 217.
[2] M. Kobayashi et al., Fusion Eng. Des. 87 (2012) 471.

採択課題番号 24083 核融合炉トリチウム増殖材中トリチウムの移行過程に及ぼす照射効果 共同通常
（静岡大・理・放射研）奥野 健二、大矢 恭久、小林 真、川崎 淨貴、藤島 徹生、宮原 祐人
内村 大道、田口 僚久、戸田 健介、三浦 遼（京大·原子炉）山名 元、藤井 俊行、上原 章寛、中野 幸廣

CO4-14

Absorption Spectrum of Water in the Terahertz Region
Using a Near-Field Aperture Probe

T. Takahashi, and S. Kimura 1, 2
Research Reactor Institute, Kyoto University
UVSOR Facility, Institute for Molecular Science2
School of Physical Sciences, The Graduate University
for Advanced Studies
1

INTRODUCTION: The basic properties of thetechnique of near-field THz-wave microscopy has been
experimentally investigated by our group [1-3]. This
technique is a characteristic application of coherent
radiation emitted from a relativistic electron beam, andprovides high spatial resolution below the diffraction
limit. In the previous report absorption spectra of cancer
tissues were observed at around 11 cm-1 [4]. In order toinvestigate the origin of the absorption we have measured
absorption spectra of pure water using a near-field
aperture probe with coherent transition radiation (CTR)
in this report.
EXPERIMENTAL PROCEDURES: The experiment
was performed at the coherent radiation beamline [5] atthe 40-MeV L-band linac of the Research Reactor
Institute, Kyoto University. The width of the macro pulse
and the repetition rate of the electron beam were 47 ns
and 46 Hz, respectively. The charge of a bunch was 1.2
nC. The THz-wave source was CTR emitted from analuminum foil with a thickness of 15-m. The thicknessof a sheet of paper tissue soaked in water was 50 m andwas put between two sheets of polyvinylidene chloride
film 11 m thick as shown in Fig. 1. The size of theaperture of the scanning probe was 775 m. The spectraof CTR were measured by a Martin - Puplett typeinterferometer.
RESULTS: The observed spectra with the aperture probe
were shown in Fig. 2. The absorption can be seen ataround 10 cm-1 in the spectra both of Kimwipes andtissue soaked in water. This absorption band to date has
not been known in the THz spectroscopy. On the other
hand, the spectra without the aperture probe were shownin Fig. 3. The absorption band has not been observed.
The size of THz wave was 10 mm on the sample.
Therefore, the absorption strength at around 10 cm-1
depends on the irradiation size of THz wave. In order toinvestigate the origin of the absorption, the theoreticalexamination of the molecular dinamics in water isnecessary.

ACKNOWLEDGMENTS: This work was partly
supported by Quantum Beam Technology Program of
MEXT, Japan.
REFERENCES:[1] T. Takahashi, et al., KURRI-PR 2008 CO4-10.
[2] T. Takahashi, et al., KURRI-PR 2009 CO4-8.
[3] T. Takahashi, et al., KURRI-PR 2010 CO4-7.
[4] T. Takahashi, et al., KURRI-PR 2011 CO4-7[5] T. Takahashi, et al., Rev. Sci. Instrum. 69 (1998)
3770.

Fig.1 The photograph of the sample. The paper tissue
soaked in water was put between two sheets ofpolyvinylidene chloride film.

■ Kimwipes● tissueFig.2 Observed absorption spectra of transmitted
THz wave with the aperture probe.
● tissue■ Kimwipes(100 m)

Fig.3 Observed absorption spectra of transmitted THz
wave without the aperture probe. The size of THz wave
on the sample was 10 mm.

採択課題番号 24084 コヒーレント遷移放射を用いたミリ波近接場イメージング
分光法に関する研究（分子研）木村真一（京大・原子炉）高橋俊晴

共同通常

CO4-15

Property of Coherent Transition Radiation Emitted from a Pair ofWire-Grid Radiators

T. Takahashi
Research Reactor Institute, Kyoto University
INTRODUCTION: For the spectroscopic purpose,
various types of coherent radiation emitted from a
relativistic electron beam have attracted a considerable
attention as a new and powerful light source in theTHz-wave region. Coherent transition radiation (CTR) is
one of such a light source. Whereas synchrotron radiation
has linear polarization along an electron orbit, the electric
vector of transition radiation (TR) emitted from a
metallic screen is axially symmetric with respect to the
trajectory of an electron beam. Therefore, CTR is usually
utilized as a non-polarized light source in the
spectroscopic application. However, circularly polarized
light has been useful in the circular dichroism
spectroscopy. Shibata et al. has developed a technique ofgeneration of circularly polarized THz-wave radiation
with the phase difference between the forward TR andthe backward TR [1]. However, it was difficult to control
the polarization degree because the geometricalarrangement was important in order to generate both thelinearly polarized the forward and the backward TR. In
the previous report [2] the property of the linearlypolarized CTR with a radiator of a wire grid wasexperimentally investigated in order to develop a newtechnique of generation of circular polarized THz
radiation. In this report a pair of wire-grid radiators withthe different polarization has been used in order toeliminate the effect of the emission length.
EXPERIMENTAL PROCEDURES: The experiment
was performed at the coherent radiation beamline [3] atthe 40-MeV L-band linac of the Research Reactor
Institute, Kyoto University. The width of the macro pulse
and the repetition rate of the electron beam were 33 ns
and 60 Hz, respectively. The average current of theelectron beam was 3 A. As the radiator of forward andbackward CTR, wire-grid polarizers 10 m thick with 25
m spacing were used, respectively. The direction of gridof the first polarizer was horizontal and that of the second
one was vertical. The spectrum of CTR was measured by
the Martin-Puplett type interferometer.
RESULTS: The observed spectra, which were measured
as varying the distance between the forward andbackward radiators, are shown in Fig.1. The distance isusually called the emission length. The observed spectra

採択課題番号24085

are similar regardless of the emission length. Figure 2
shows the dependence of intensity on the emission length
at some wavelengths in fig.1. When the emission lengthis far shorter than the formation length, the intensity of
CTR emitted from the metallic foil is proportional to thesquare of the emission length [4]. Here, the formation
length in the millimeter-wave region is longer than 15 m
for the 40-MeV electron beam. It became clear that the
CTR with horizontal polarization emitted from theforward grid is not reflected to the spectrometer by thesecond vertical grid and the observed intensity depends
on the distance between the forward Ti window and thesecond grid.
REFERENCES:[1] Y. Shibata et al., Rev. Sci. Instrum. 72 (2001) 3221.
[2] T. Takahashi, et al., KURRI-PR 2009 CO4-5.
[3] T. Takahashi et al., Rev. Sci. Instrum. 69 (1998)
3770.
[4] Y. Shibata et al., Phys. Rev. E 49 (1994) 785.

Fig.1. The observed spectra as varying the emission
length (L).

Fig.2. The relation between the observed
intensity and the emission length at eachwavenumber in fig.1.

コヒーレント遷移放射を用いたミリ波領域
高時間分解分光法と円偏光の制御に関する研究（京大・原子炉）高橋俊晴、窪田卓見

共同通常

CO4-16

Charaterizations of Dynamic Behavior for Organic Solar Cells under
High-Energry Secondary Electrons by 60Co Beams

M. Oita, K Nakata1 and Y. Sakurai2

EXPERIMENTS: The samples used in this work are
Si-SCs (#0906005B, Mimatsu Audio Corp, Japan) and
OSCs. The surfaces of are coated by epoxy resin. The
OSCs fabricated by TiO2 photoelectrodes which wereprepared by screen-printing a TiO2 paste (Ti-Nanoxide
T/SP, Solaronix SA) on fluorine-doped indium tin oxide/glass (FTO) substrates (Solaronix SA). The TiO2
photoelectrodes were annealed at 200 °C for 10 min, andthen at 500 °C for 30 min, resulting in anatase films.
Multiple heating steps were performed to avoid crackingof the TiO2 layer. The above TiO2 photoelectrode wassoaked in a solution of dye, and then dried under an air
flow. A 50-μm-thick Himilan (R) film was used to assemble the TiO2 electrode with a Pt-sputtered FTO electrode (the thickness of the Pt layer was 100 nm). The
space between the electrodes was filled with a mixed
electrolyte in acetonitrile. All of the samples were irradiated by 60Co beams ranged from 50 Gy to 50 kGy at
KUR 60Co Gamma-ray Irradiation facility. To evaluate
the degradation of the samples, conversion efficiencies
and other electric characteristics were measured by a solar simulator (YSS-T150A, YAMASHITA DENSO
Corp.) before and after irradiation.

OSCs
SiSCs

3.0

Degradation of conversion efficiency (%)

INTRODUCTION: Solar cells have been used as
power sources by many environmental circumstances,and played an important role in a wide range of scientificresearch and space development applications. For theapplication of satellites in space, understanding the tolerances and degradations of such cells by radiation in
space is important issues [1-3]. In contrast, for medical
applications for radiation dosimetry, Si-based semiconductor detectors are often used [4,5]. Recently, organic
solar cells (OSC) have been widely developed due to low
production costs and roll-to-roll manufacturing on flexible substrate compared to Si-based cells [6,7]. Furthermore, OSCs allow the evaluation of the radiation dose for
medical practices such as radiation examinations andradiotherapy. However, the development and applicationof radiation detectors using solar cells are still investigated. In this work, the authors investigated the degradations and tolerance of OSCs compared to single-crystal
Si-based solar cells (Si-SCs) under high-energy secondary electrons by 60Co beams.

RESULTS: Fig. 1 shows the degradation of conversion
efficiencies for OSCs as compared to Si-SCs by radiation.
There were no significant changes between OSCs and
Si-SCs less than 5 kGy. Fig. 2 shows the degradationsof the short-circuit current density for OSCs as comparedto Si-SCs by radiation. The degradations of the output
current for OSCs were observed about less than 1% / kGy.
In summary, high-energy secondary electrons by 60Co
beams irradiated and investigated the radiation toleranceof OSCs. These results reveal that the dosimetry devices
using OSCs would be feasible for medical application.

2.5
2.0
1.5
1.0
0.5
0.0
-0.5
-1.0
-1.5
-2.0
-2.5
-3.0
100

1000

10000

Dose (Gy)Fig. 1. The degradation of conversion efficiency for OSCsand Si-SCs under secondary electrons by 60Co beams.
Degration of short-circuite current density (mA/cm2)

Graduate School of Health Sciences, Okayama University
1
Department of Applied Biological Science, Faculty of
Science and Technology, Tokyo University of Science2
Research Reactor Institute, Kyoto University

OSCs
SiSCs

3.0
2.5
2.0
1.5
1.0
0.5
0.0
-0.5
-1.0
-1.5
-2.0
-2.5
-3.0
100

1000

10000

Dose (Gy)Fig. 2. Degradation of short-circuit current density for
OSCs and Si-SCs under secondary electrons by 60Co beams.

REFERENCES:[1] A. Khan et al., J. Appl. Phys., 87 (2000) 2162.
[2] J. Haapamaa et al, Solar Energy Materials & Solar
Cells, 66 (2001) 573.
[3] A. Khan et al., Solar Energy Materials & Solar Cells,
75 (2003) 271.
[4] Bo. Nilsson et al., Radiotherapy and Oncology, 11(1988) 279.
[5] D. Menichelli et al., Nucl. Instr. and Meth. A, 583(2007) 109.
[6] M. Manceau et al., Organic Electronics, 12 (2011)
566.
[7] J-W Kang et al., Solar Energy Materials & Solar Cells,
103 (20127) 76.

採択課題番号 24095 高エネルギー粒子線による有機系太陽電池の動的挙動に関する研究 共同通常
（岡山大・保）笈田将皇（東京理科大・理工）中田一弥（京大・原子炉）櫻井良憲

CO4-17 Activation Analysis of Tungsten Deposited on Graphite Tiles of JT-60U Tokamak
Y. Ueda, Y. Meichang, K. Jo1 and M. Fukumoto2

5

10

4

10

3

10

2

10

1

10

0

Count

Graduate School of Engineering, Osaka University
1
Graduate School of Science, Kyoto University
2
Japan Atomic Energy Agency

10

INTRODUCTION: Tungsten local transport in the
JT-60U tokamak device (JAEA) has been studied. Tungsten coated CFC tiles were installed in the outer divertor
position, on which outer strike points did not normally
stay. Tungsten on inner divertor tiles existed in the thickcarbon deposition layer (more than 100 µm in thickness),which makes estimation of total amount of tungsten deposition difficult by conventional surface analysis methods(e.g. XPS, AES). In order to measure the total amount oftungsten in the thick carbon deposition, a neutron activation method by the KUR fission reactor was employed. In
the fiscal year of 2012, first trial of the activation experiments of carbon samples containing tungsten deposits
was done.

RESULTS: Unfortunately, graphite samples with thedimensions of 10 x 10 x 1 did not have enough strength
to withstand a transfer process to KUR by compressed air.
They were cracked and given up for activation measurement. Fig. 1 showed gamma spectrum of the activatedpure W sample. No gamma rays from 185W were observed, probably because neutron exposure time was too
short to make enough activation. On the other hand, radiation from a short lived isotope (187W) almost disappeared in this measurement. Since total amount of tungsten deposition on W samples are similar or less than thatof the pure tungsten, it turns out that this activation analysis method is not useful to tungsten deposition measurement on JT-60 tiles.
The other possibility is to use the shot lived isotope

採択課題番号 24100

200

400

600
800
1000
Energy (keV)

1200

1400

1600

2

10

1

10

0

846

551

773

10

686

3

JT60 sample (P.8 divertor)

618

10

Normalized W foil

479

10

4

134

5

72

10

59 ( K1)

Fig.1 Gamma ray spectrum from a puretungsten sample

Yield count/keV

EXPERIMENTS: The samples were prepared in a
JAEA Naka cite. Since C deposition layers are very fragile, surfaced of the tiles were covered by sticky transparent tapes for protection. Sizes of the samples were about
10 x 10 x 1 mm. Since graphite base materials containvery few impurities, activation elements in the samples
are mostly tungsten, which was confirmed by a previous
neutron activation experiment [1].
Three graphite samples and one pure tungsten sample(0.5 mg) were installed in a plastic capsule, which was
exposed to neutrons by 1MW KUR operation for fourhours. Then it was kept for about three months to wait forcooling down of short lived tungsten isotopes (mainly
187
W, 23.5 hours), leaving long lived isotopes (mainly
185
W, 75 days). Gamma spectrum was measured by a Ge
semiconductor detector.

0

0

200

400

600

Energy keV

800

1000

Fig. 2 Gamma ray spectrum from a neutron-activated sample by FNS. Gamma mainly
187
from W was detected.
(187W), which will emit stronger gamma ray signal than
185
W. An example is shown in Fig. 2. These data weretaken also by a neutron activation method previously
performed at FNS in JAEA. In Fig. 2, gamma spectrum
from pure W (larger signal) and that from a JT-60U sample. Several lines (e.g. 479 keV, 686 keV etc.) from 187W
were clearly observed in this experiment. In next experiment, we plan to use these lines to determine tungsten
deposition on JT-60U samples. In addition, it is importantto find more suitable sample size (probably thicker samples are better) and to insert shock absorber in a capsule
to avoid breakdown of graphite samples.

REFERENCES:[1] Y. Ueda et al., Nucl. Fusion 49 (2009) 065027 (7pp).

JT-60 トカマク装置の炭素タイル上に堆積したタングステンの放射化分析（阪大・工）上田良夫、余 美昌（京大・原子炉）徐 虬（原子力機構）福本正勝

共同通常

CO4-18

Ground Plane of the B–3 Beam Port of KUR

K. Mori, H. Yoshino, S. Sato1, S. Muto1, K. Iwase2, S.
Tomihira3, T. Fukunaga and Y. Kawabata
Research Reactor Institute, Kyoto University (KURRI)
1
High Energy Accelerator Research Organization (KEK)2
Department of Materials and Engineering, Ibaraki University
3
Graduate School of Engineering, Kyoto University
INTRODUCTION: The B–3 beam port of Kyoto
University Research Reactor (KUR) had long been used
as a four-circle single-crystal neutron diffractometer(4CND). For the last decade, however, the 4CND was
so old that its research activity on neutron science wasquite low. Therefore, the 4CND needed to be replaced
and a new neutron diffractometer has been required at the
B–3 beam port. Meanwhile, the growing demand to
study the atomic structure of the various kinds of materials promotes the use of neutron scattering techniques.
In particular, the neutron (powder) diffraction is a powerful tool to determine the positions of light elements(e.g., hydrogen and lithium) in energy storage materials
such as hydrogen absorbing materials and lithium-ion
batteries.
Here, we report the ground plane of the B-3 beam port
of KUR, particularly the “compact” multipurpose neutron
diffractometer. In addition, we have a plane to utilize
for the study of the neutron detector development by thedata acquisition group of the neutron science division of
KEK (KEK–KENS DAQ group) at the B-3 beam port, as
we mention below.
DESIGN CONCEPT OF B–3: Figure 1 shows theschematic perspective view of the compact multipurpose
neutron diffractometer. The neutron wavelength (λ),
which is monochromatized by the (220) plane of a Cu
single crystal, is 1 Å. To cover the detector area (6 º ≤2θ ≤ 150 º), 36 3He tube detectors (1/2 inch diameter)
will be used. The distances from the monochromator to
the sample and from the sample to the detector will be
1.9 m and 1.2 m, respectively. In the second period of
the neutron beam time in fiscal 2012, the preliminary
neutron diffraction experiments were conducted withstandard powder samples (e.g., Ni) and hydrogen absorbing alloy ones, using 6 3He tube detectors, instead ofan old BF3 detector of the 4CND. In spite of highbackground intensities, we succeeded to observe theirseveral Bragg reflections, which could be indexed on thebasis of λ = 1 Å.
DEVELOPMENT OF NEUTRON DETECTORSYSTEM: The B–3 beam port has a wide space aroundthe sample; therefore we can easily install any other system. The KEK–KENS DAQ group has used the B–3
beam port to assess their new 6Li-glass neutron detector
system, LiTA12, as shown in Fig. 2. The LiTA12 system consists of a 6Li-glass neutron detector with a multianode photo multiplier tube (MA–PMT), an amplifier,and an analog-to-digital converter (ADC) board. The
further investigations are now in progress.

Fig. 1. The schematic perspective view of the compact
multipurpose neutron diffractometer at the B–3 beam port
of KUR.

Fig. 2. New 6Li-glass neutron detector system, LiTA12,
which has been developed by the KEK–KENS DAQ
group.
ACKNOWLEDGEMENTS: We would like to thankthe KEK–KENS for providing the equipment for neutron
diffraction experiments; 3He tube detectors, etc. We are
grateful to Ms. T. Mori for drawing the schematic illustrations of the compact multipurpose neutron diffractometer.

採択課題番号 24106	
  材料研究および中性子検出器開発を目的とした共同即時	
 多目的型簡易粉末回折装置の建設	
 （京大・原子炉）森	  一広、吉野泰史、福永俊晴、川端祐司（高エネ研）佐藤節夫、武藤	  豪	
 （茨城大・工）岩瀬謙二（京大院・工）冨平昌吾	
 CO4-19

Radiation Anomaly Invesitgation of Nano-Satellite “Horyu-II”

Y. Okumura, H. Masui, M. Cho and K. Takamiya1
Kyushu Institute of Technology
1
Research Reactor Institute, Kyoto University
INTRODUCTION: Recently universities and venturebusinesses actively develop micro/nano-satellites.
Horyu-II launched in May 2012 suffered anomaly byradiation. Radiation test is important to investigate thecause. Conventional radiation test needs an accelerator.
The cost is too high for micro/nano-satellites. Radiation
test with californium-252 will give us an affordable solution.

RESULTS: While the targets were irradiated, we detected malfunction of the H8 processors. Fig.3 shows thecurrent consumption of the circuit boards. First, the radiation source was placed over H8-Main that handles dataprocessing. During the section (i), the experimental
boards were working normally. The jump in the current
near 250s is due to the start of the communication. In
section (ii), malfunction on H8-Main occurred and at thesame time, the current jumped by 0.1 A. We tried to reset
H8-Main via a command, but failed. We moved the radiation source over H8-COM that handles communication.
In section (iii), H8-COM malfunctioned and the current
also jumped by another 0.1A.

EXPERIMENTS: The purpose of the test is to detect
SEE (Single Event Effect) using californm-252 and reproduce the anomaly phenomenon of Horyu-II. The
anomaly occurred in H8 microcomputer which processed
all the data of the satellite. We used a spare board of
Horyu-II and irradiated 2 points shown in Fig. 1. The
plastic packages were removed to make radiation particles penetrating.

Fig. 3.
TargetFig. 1. Irradiation targets
The experimental schematic is illustrated in Fig. 2 (Sideview of the circuit board). We monitored the current
consumed by the circuit boards.
ion of OBC and all system.

Consumption current of the satellite system

Fig. 4 summarizes Horyu-II’s anomaly observed in orbit.
The upper figure is Normal mode. The middle figure is
the first anomaly observed. The sensor data in the downlink telemetry became frozen. This phenomenon can be
explained by the malfunction of H8-Main. The bottom
figure shows the second anomaly. Horyu-II couldn’t send
even the frozen sensor data back. This phenomenon canbe explained by the malfunction of H8-COM. Therefore,
we conclude Horyu-II’s anomaly was caused by single
event effect of H8 processors.

Fig. 4. Failure mode

Fig. 2. Experiment schematics

REFERENCES:[1] Stephen J H, Sanderson T K, Mapper D,
Farren J. IEEE Trans. Nucl. Sci., 1984,
NS-31(6): 106

採択課題番号24108
ｶﾘﾌｫﾙﾆｳﾑ線源を使用した衛星搭載用ｵﾝﾎﾞｰﾄﾞｺﾝﾋﾟｭｰﾀに発生する
 ｼﾝｸﾞﾙｲﾍﾞﾝﾄの模擬試験および試験方法の確立
（九工大・先端）奥村 裕太、増井 博一、趙 孟佑（京大・原子炉）高宮 幸一

共同即時