第回 フ ラ ー レ ン・ナノ チュー ブ・グ ラ フェン 総 合 シンポ ジウ ム 講 演 要 旨 集

58
44

令
平和
成２年３月 日～
〜 日

25

15
11

18
13

F NTG

Research Society

第 58 回フラーレン・ナノチューブ・グラフェン
総合シンポジウム

The 58th Fullerenes-Nanotubes-Graphene General Symposium

講演要旨集
Abstracts
2020 年 3 月 15 日（日） ～ 18 日（水）東京大学 伊藤国際学術研究センター
The University of Tokyo, ITO INTERNATIONAL RESEARCH CENTER
主催 フラーレン・ナノチューブ・グラフェン学会
The Fullerenes, Nanotubes and Graphene Research Society
共催 ・ 後援
日本化学会
The Chemical Society of Japan東京大学大学院工学系研究科 School of Engineering, The University of Tokyo
東京大学 CIAiS Consortium for Innovation of Advanced Integrated Science (UTokyo)
東京大学 GMSI Graduate Program for Mechanical Systems Innovation (UTokyo)
JST-CREST ([Thermal Control]Creation of Innovative Core Technologies for Nanoenabled Thermal Management)
協賛
日本物理学会
応用物理学会
高分子学会
電気化学会

The Physical Society of JapanThe Japan Society of Applied Physics
The Society of Polymer Science, JapanThe Electrochemical Society of Japanグラフェンの量産化に向けて…
Neutron▼概要▼
Roll-to-Roll (R2R)
ロール状に巻いた金属ホイルを、巻き取りな
がら連続的にグラフェンを成長可能な量産用装置◆特徴◆• 連続成長• 生産能力 20,000 m2 / year
• Cuホイル及びSteelホイルの両方に対応• 大気環境で成長可能で、真空チャンバ不要• 生産コストの大幅削減

CCS 2D & NOVO

BM300T▼概要▼
2D材料及びグラフェンの成長装置▼概要▼
ウェハ基板上CNT及びグラフェン
成長装置

◆特徴◆
• Closed Coupled Showerhead(CCS)
技術を適用• 成長温度は1400℃まで昇温可能• 基板に直接2D材料またはグラフェンを成長
可能• プラズマ機能装備• 多種原料を搭載可能(hBN, MoS2, WSe2)◆特徴◆• 12”及び8” wafer 自動搬送対応• プラズマ機能装備• High 2D/G > 2.5の高品質を達成

アイクストロン株式会社 www.aixtron.com〒140-0001 東京都品川区北品川1-8-11 Daiwa品川Northビル9F
E-mail: japaninfo@aixtron.com Phone: 03-5781-0931 Fax: 03-5781-0940

Our technology. YOUR FUTURE

Abstract of
The 58 Fullerenes-Nanotubes-Graphene General Symposiumth

Sponsored by : The Fullerenes, Nanotubes and Graphene Research Society
Co-Sponsored by : The Chemical Society of Japan

School of Engineering, The University of Tokyo
Consortium for Innovation of Advanced Integrated Science (UTokyo)
Graduate Program for Mechanical Systems Innovation (UTokyo)
JST-CREST ([Thermal Control]Creation of Innovative Core Technologies
for Nano-enabled Thermal Management)

Supported by : The Physical Society of JapanThe Japan Society of Applied Physics
The Society of Polymer Science, JapanThe Electrochemical Society of Japan

Date : March 15th(Sun.) – March 18th(Wed.), 2020
Place : The University of Tokyo, ITO INTERNATIONAL RESEARCH CENTER

7-3-1 Hongo, Bunkyo-ku, Tokyo 113-8656

Presentation Time : Special Lecture (25 min presentation + 5min discussion)

Invited Lecture (10 min presentation + 5min discussion)
General Lecture (10 min presentation + 5min discussion)
Poster Preview (1 min presentation without discussion)

第 58 回フラーレン･ナノチューブ･グラフェン総合シンポジウム
講演要旨集
主催 : フラーレン･ナノチューブ･グラフェン学会
共催･後援 : 日本化学会
東京大学大学院工学系研究科
東京大学 CIAiS東京大学 GMSI
JST-CREST（「熱制御」ナノスケール･サーマルマネージメント基盤技術の創出）
協賛 : 日本物理学会、応用物理学会、高分子学会、電気化学会
日時 : 令和 2 年 3 月 15 日(日)～3 月 18 日(水)場所 : 東京大学 伊藤国際学術研究センター〒113-8656 東京都文京区本郷 7-3-1

伊藤謝恩ホール

発表時間 : 特別講演
（発表 25 分 + 質疑応答 5 分）
招待講演
（発表 10 分 + 質疑応答 5 分）
一般講演
（発表 10 分 + 質疑応答 5 分）
ポスタープレビュー（発表 1 分・質疑応答 なし）

展示団体御芳名 (五十音順、 敬称略）
(株）島津製作所(株）セントラル科学貿易
テレダイン・ジャパン(株）日本シノプシス（同）（株）日本レーザー
フィルジェン（株）(株）名城ナノカーボン

広告掲載団体御芳名 (五十音順、 敬称略）
アイクストロン(株)エクセルソフト（株）(株) コロナ社(株）セントラル科学貿易
ソーラボジャパン（株）
テレダイン・ジャパン(株）日本電子（株）（株）日本レーザー

Contents
Time Table ・・・・・・・・・・・・・・・・・・ i
Chairperson ・・・・・・・・・・・・・・・・・iii
ProgramJapanese ・・・・・・・・・・・・ iv
English ・・・・・・・・・・・・xviii
Abstracts
Special Lecture ・・・・・・・・・・ 1
Invited Lecture ・・・・・・・・・ 9Commemorative Session ・・・・・・ 11
General Lecture ・・・・・・・・・ 17
Poster Preview ・・・・・・・・・・ 45
Author Index ・・・・・・・・・・・・・・・・ 137

目次
早見表 ・・・・・・・・・・・・・・・・・・・ i
座長一覧・・・・・・・・・・・・・・・・・・・iii
プログラム 和文・・・・・・・・・・・・・・・ iv
英文・・・・・・・・・・・・・・xviii
講演予稿
特別講演・・・・・・・・・・・・・ 1
招待講演・・・・・・・・・・・・・ 9記念セッション・・・・・・・・・・11
一般講演・・・・・・・・・・・・・17
ポスター発表・・・・・・・・・・・45
発表索引・・・・・・・・・・・・・・・・・・ 137

プログラム早見表
３月１５日 （日）受付開始 8：30～
講演開始 9：30～
9:30 招待講演（Esko I. Kauppinen）9:30-9:45
9:45
一般講演 3件(ナノチューブの生成と精製 ・ナノチューブの応用） 9:45-10:30

10:30
10:45

休憩 10:30-10:45
一般講演 3件(ナノチューブの応用）

11:30
12:15

13:30

10:45-11:30
ポスタープレビュー( 1P-1 ～ 1P-31 )11:30-12:15
昼食(幹事会）
12:15-13:30
ポスターセッション【 多目的スペース 】
13:30-15:15

３月１６日 （月）３月１７日 （火）受付開始 8：30～
講演開始 9：00～
9:00 特別講演 (Jaime C. Grunlan)
9:00-9:30
9:30
一般講演 3件受付開始 8：30～
講演開始 9：00～
9:00 特別講演 (YuHuang Wang)
9:00-9:30
9:30
一般講演 3件(ナノチューブの物性 ・
原子層）
9:30-10:15

10:15
10:30

休憩 10:15-10:30
特別講演 （中村 潤児）
10:30-11:00
11:00 一般講演 2件 (原子層 ・

15:45
16:30
17:00

12:15

13:30

18:00
18:15

ポスタープレビュー( 2P-1 ～ 2P-30 )11:30-12:15
昼食
12:15-13:30

ポスターセッション【 多目的スペース 】
13:30-15:15

15:15

授賞式
15:15-16:00(グラフェン生成 ・ 原子層 ・グラフェンの物性）15:45-16:30

16:00

記念セッション
（阿知波 洋次）（斎藤 晋）（飯島 澄男）
16:00-17:15
休憩 17:15-17:30
記念セッション
（大澤 映二）（大塚 雅昭）（磯部 寛之）17:30-18:45

特別講演 （窪田 芳之）
16:30-17:00
一般講演 4件
17:00-18:00
休憩 18:00-18:15
チュートリアル講師： （松田 一成）
京都大学【 伊藤謝恩ホール 】
18:15-19:45

ナノチューブの物性） 11:00-11:30

11:30
12:15

13:30

13:30-14:00 若手奨励賞候補審査優先時間

特別講演 （中野 匡規）
15:15-15:45
一般講演 3件(内包ナノチューブ ・金属内包フラーレン ・ その他）

10:15
休憩 10:15-10:30
10:30 特別講演 (Christophe Bichara)
10:30-11:00
11:00 一般講演 2件 (その他 ・グラフェンの応用） 11:00-11:30

11:30

13:30-14:00 若手奨励賞候補審査優先時間

15:15(ナノチューブの応用 ・ ナノチューブの生成と精製） 9:30-10:15

17:15
17:30

ポスタープレビュー( 3P-1 ～ 3P-31 )11:30-12:15
昼食
12:15-13:30

ポスターセッション【 多目的スペース 】
13:30-15:15
13:30-14:00 若手奨励賞候補審査優先時間

15:15

特別講演 （Yan Li）
15:15-15:45
15:45 一般講演 2件 (ナノチューブの物性 ・ ナノホーン） 15:45-16:15

16:15
16:45

特別講演 （千賀 亮典）
16:15-16:45
一般講演 3件(原子層)
16:45-17:30

17:30

18:45

19:45
講演会場 伊藤謝恩ホール
特別講演 発表２５分・質疑５分
招待講演 発表１０分・質疑５分
一般講演 発表１０分・質疑５分
ﾎﾟｽﾀｰﾌﾟﾚﾋﾞｭｰ 発表１分・質疑なし

３月１８日 （水）第１４回ﾅﾉｶｰﾎﾞﾝ実用化推進研究会【 伊藤謝恩ホール 】

10:00-18:00

iTime table
March 15 (Sun.)
Registration begins at 8:30
Lectures begin at 9:30

March 16 (Mon.)

March 17 (Tue.)

Registration begins at 8:30
Lectures begin at 9:00
9:00
Special Lecture

Registration begins at 8:30
Lectures begin at 9:00
9:00
Special Lecture(Jaime C. Grunlan) 9:00-9:30

9:30 Invited Lecture（Esko I. Kauppinen）9:30-9:45
9:45
General Lectures [3]

9:30

10:30
10:45

9:45-10:30

Coffee Break 10:30-10:45
General Lectures [3](Applications of nanotubes）

11:30
12:15

13:30

15:15

10:45-11:30
Poster Preview( 1P-1 through 1P-31 )11:30-12:15
Lunch(Administrative meeting)
12:15-13:30
Poster Session【 Event Space 】
13:30-15:15

10:15
10:30

9:30-10:15

Coffee Break 10:15-10:30
Special Lecture（Christophe Bichara）10:30-11:00

11:00 General Lectures [2] (Other topics
・ Properties of nanotubes） 11:00-11:30

・Applications of graphene） 11:00-11:30

11:30
12:15

13:30

Poster Preview( 2P-1 through 2P-30 )11:30-12:15
Lunch
12:15-13:30

Poster Session【 Event Space 】
13:30-15:15

11:30
12:15

13:30

Poster Preview( 3P-1 through 3P-31 )11:30-12:15
Lunch
12:15-13:30

Poster Session【 Event Space 】
13:30-15:15

During 13:30-14:00, please give

During 13:30-14:00, please give

During 13:30-14:00, please givepriority to selection of candidates

priority to selection of candidates

for Young Scientist Poster Award

for Young Scientist Poster Award

for Young Scientist Poster Award

Special Lecture

15:15

Award Ceremony
15:15-16:00

16:00

Commemorative Session（Yohji Achiba）（Susumu Saito）（Sumio Iijima）

Special Lecture
General Lectures [4](Endohedral nanotubes ・Endohedral metallofullerenes ・Other topics)
17:00-18:00

Coffee Break 18:00-18:15
Tutorial
Lecturer :（Kazunari Matsuda）
Kyoto University【 Ito Hall 】
18:15-19:45

15:15

Special Lecture（Yan Li） 15:15-15:45

15:45 General Lectures [2] (Properties

General Lectures [3]（Yoshiyuki Kubota） 16:30-17:00

18:00
18:15

10:15
10:30

（Junji Nakamura） 10:30-11:00

・ Properties of graphene） 15:45-16:30

17:00( Applications of nanotubes ・ Formation andpurification of nanotubes）

priority to selection of candidates(Graphene synthesis・Atomic Layers

16:30

Coffee Break 10:15-10:30
Special Lecture(YuHuang Wang) 9:00-9:30
General Lectures [3]11:00 General Lectures [2] (Atomic Layers（Masaki Nakano） 15:15-15:45

15:45

9:30

(Properties of nanotubes ・Atomic Layers） 9:30-10:15(Formation and purification of nanotubes・Applications of nanotubes)

General Lectures [3]

17:15
17:30

16:00-17:15
Coffee Break 17:15-17:30
Commemorative Sessionof nanotubes・Nanohorns) 15:45-16:15

16:15

Special Lecture（Ryosuke Senga） 16:15-16:45

16:45

General Lectures [3](Atomic Layers）

16:45-17:30
17:30（Eiji Osawa）（Masaaki Otsuka）（Hiroyuki Isobe）

17:30-18:45
18:45

19:45
March 18 (Wed.)
The 14th NanoCarbon Application Forum【 Ito Hall 】

10:00-18:00

Place : Ito Hall
Special Lecture : 25 min (Presentation) + 5 min (Discussion)
Invited Lecture : 10 min (Presentation) + 5 min (Discussion)
General Lecture : 10 min (Presentation) + 5 min (Discussion)
Poster Preview : 1 min (Presentation)ii

座長一覧 (Chairpersons)
3月15日 (日)セッション
招待講演(Esko I. Kauppinen）
一般講演
一般講演
ポスタープレビュー
特別講演(中野 匡規）
一般講演
特別講演(窪田 芳之）
一般講演
チュートリアル(松田 一成）

(敬称略）

時
間
9:30 ～ 9:45
9:45 ～ 10:30
10:45 ～ 11:30
11:30 ～ 12:15
15:15 ～ 15:45
15:45 ～ 16:30
16:30 ～ 17:00
17:00 ～ 18:00
18:15 ～ 19:45

座
長
丸山 茂夫
田中 丈士
杉目 恒志 / 井ﾉ上 泰輝
北浦 良
湯田坂 雅子
松尾 豊
丸山 茂夫

3月16日 (月)セッション
特別講演(Jaime C. Grunlan）
一般講演
特別講演(中村 潤児）
一般講演
ポスタープレビュー
記念セッション（阿知波 洋次）（斎藤 晋）（飯島 澄男）祝辞紹介
記念セッション（大澤 映二）（大塚 雅昭）（磯部 寛之）時
間
9:00 ～ 9:30
9:30 ～ 10:15
10:30 ～ 11:00
11:00 ～ 11:30
11:30 ～ 12:15
16:00 ～ 17:15

17:30 ～ 18:45

座
長
柳 和宏
宮内 雄平
高井 和之
中西 勇介 / 丸山 実那
岡田 晋

若林 知成
若林 知成 / 小澤 理樹
菅井 俊樹
竹延 大志

3月17日 (火)セッション
特別講演(YuHuang Wang）
一般講演
特別講演(Christophe Bichara）
一般講演
ポスタープレビュー
特別講演(Yan Li）
一般講演
特別講演(千賀 亮典）
一般講演

時
間
9:00 ～ 9:30
9:30 ～ 10:15
10:30 ～ 11:00
11:00 ～ 11:30
11:30 ～ 12:15
15:15 ～ 15:45
15:45 ～ 16:15
16:15 ～ 16:45
16:45 ～ 17:30

iii

座
長
宮内 雄平
柳 和宏
千足 昇平
小澤 大知 / 岡田 光博
Don N. Futaba項 榮

３月 １５日 （日）特別講演
発表 ２５分 ・ 質疑応答 ５分
招待講演
発表 １０分 ・ 質疑応答 ５分
一般講演
発表 １０分 ・ 質疑応答 ５分
ポスタープレビュー
発表 １分 ・ 質疑応答 なし

招待講演 ( 9:30-9:45 )1I-1

FC-CVD synthesis of CNTs from methane for transparent conductor applications

9* Esko I. Kauppinen, Qiang Zhang, Datta Sukanta, Hua Jiang

一般講演 ( 9:45-10:30 )ナノチューブの生成と精製 ・ ナノチューブの応用
1-1

超分子化学による半導体性SWNTのone-pot分離

17* 中嶋 直敏
1-2

1cmを超える長尺CNTフォレストの高速成長

18* 桜井 俊介, 辻 享志, 山田 真保, 畠 賢治, Futaba Don
1-3

ホタル由来ルシフェリン/ルシフェラーゼ反応を利用したCNTの発光

19* 田中 丈士, 樋口 麗保子, 平塚 淳典, 片浦 弘道＞＞＞＞＞＞＞ 休憩 ( 10:30-10:45 ) ＜＜＜＜＜＜＜一般講演 ( 10:45-11:30 )ナノチューブの応用
1-4

Selective Activation of Singlet/Triplet Reaction Paths Enabled by
Carbon-nanotube-mediated Energy Attenuation

20* Dongxin Liu, Dominik Lungerich, Satori Kowashi, Takayuki Nakamuro,
Kaoru Yamanouchi, Koji Harano, Eiichi Nakamura
1-5

Polyaromatic Anthracene Nano-tweezer on Semiconducting Carbon Nanotubes for Growthand Bridging of Perovskite Crystal Grains in Perovskite Solar Cells

21* 林 昊升, 大川 脩平, 田 日, 松尾 豊, 丸山 茂夫
1-6

Optimization of the Alignment Relay Technique for the Controlled Orientation and
Selection of Single-Walled Carbon Nanotubes

22* Monika Snowdon, Derek Schipper, Dai-ming Tang

ポスタープレビュー ( 11:30-12:15 )若手奨励賞候補
1P-1☆

（☆） 若手奨励賞候補

針状のフラーレンC70単結晶を用いた有機電界効果トランジスタ45* 山本 亮平, 平井 匡彦, 青木 伸之, 橘 勝

1P-2

Alteration of Fermi-Level of Single-Wall Carbon Nanotubes via Protein Adsorption
Observed by Ultrafast Spectroscopy☆

* Tomohito Nakayama, Takeshi Tanaka, Atsushi Hirano, Muneaki Haseiv

46

３月 １５日 （日）1P-3☆

カーボンナノチューブ複合樹脂材料の力学特性と相構造

1P-4☆

Understanding the Effect of Sulfur on the Synthesis of Carbon Nanotubes

47* 村岡 慶美, 福森 健三
48* 仲川 黎, 江戸 倫子, 杉目 恒志, 野田 優

1P-5

Evaluation of various nitrogen-doping in graphene on the performance as a supercapacitor
electrode☆

* Rohit Yadav, Prerna Joshi, Masanori Hara, Masamichi Yoshimura

1P-6

Gene expression analysis of macrophages on carbon nanohorn coated titanium☆

* Sadahito Kimura, Eri Hirata, Sari Takada, Masatoshi Sakairi, Masako Yudasaka,
Atsuro Yokoyama

1P-7

Unidirectional bright exciton transport in a WS2xSe(2-2x) alloy monolayer☆

* Masafumi Shimasaki, Taishi Nishihara, Naoki Wada, Zheng Liu, Kana Kojima,
Keisuke Shinokita, Kazunari Matsuda, Yasumitsu Miyata, Yuhei Miyauchi

49

50

51

ナノチューブの物性 【CREST】
1P-8

MoS2 ナノチューブバンドルの電子状態

52* 久間 馨, 丸山 実那, 岡田 晋, 千足 昇平, 丸山 茂夫
1P-9

Rayleigh scattering measurement of suspended SWCNTs coaxially wrapped with BNNTs

53* Satoshi Yotsumoto, Hayato Arai, Yongjia Zheng, Taiki Inoue, Rong Xiang,
Shigeo Maruyama, Shohei Chiashi
1P-10

Optical properties of inorganic nanotubes with different diameters

54* Yohei Yomogida, Yasumitsu Miyata, Kazuhiro Yanagi
1P-11

Chemical vapor deposition of one-dimensional heterostructures

55* Yongjia Zheng, Yang Qian, Ming Liu, Akinito Kumamoto, Yuichi Ikuhara,
Esko I. Kauppinen, Shohei Chiashi, Taiki Inoue, Rong Xiang, Shigeo Maruyama
1P-12h-BN上へのガス流配向CNTの合成とラマン分光測定56* 佐藤 周, 四元 聡, 番場 雅典, 井ノ上 泰輝, 丸山 茂夫, 千足 昇平
1P-13

In-Plane Thermal Conductance of Thin Films Composed of Coaxially CombinedSingle-Walled Carbon Nanotubes and Boron Nitride Nanotubes

57* Pengyingkai Wang, Yongjia Zheng, Taiki Inoue, Rong Xiang, Ahmed Shawky,
Makoto Watanabe, Anton Anisimov, Esko I. Kauppinen, Shohei Chiashi, Shigeo Maruyama

ナノチューブの応用 【CREST】
1P-14

Fabrication of ribbon-like films with highly oriented carbon nanotubes using a robotic
dispenser* Manish Pandey, Ryo Abe, Naofumi Okamoto, Yuki Sekimoto, Masakazu Nakamurav

58

３月 １５日 （日）フラーレンの化学
1P-15

ポリインのリン光：新規ポリイン誘導体検出の鍵となる探針59* 若林 知成, 北村 望, 大澤 綾人, 岡田 大貴, 鈴木 晴, 森澤 勇介, 畑中 美穂
1P-16

CuCl-Mediated Reaction of C60 with Propargylic Phosphate

60* 石塚 明日美, 前田 優, 山田 道夫

フラーレンの応用
1P-17

Catalytic activity for the reduction of 4-nitrophenol using on gadolinium oxide
nanoparticle-[C60]fullerene nanowhisker composites

61* Jeong Won Ko, Sugyeong Jeon, Weon Bae Ko

金属内包フラーレン
1P-18

Reactions of S-Heterocyclic Carbenes with Fullerenes: Preparation andCharacterization of Dithiomethano-derivatives

62* 前田 勇太, 官澤 伸治, 加固 昌寛, 山田 道夫, 前田 優, 古川 真, 赤阪 健

ナノチューブの応用
1P-19

CNT/HDPE複合材料の破断挙動の解明

63* 宇津木 孝一, 大槻 南央, 関戸 大

ナノチューブの生成と精製
1P-20

TDDFT計算により示唆される直径1nm以下のカーボンナノチューブの直線偏光レーザー
照射下の優先的安定性

64* 宮本 良之
1P-21

ナノジルコニア分散カーボンペーパー上へのカーボンナノチューブ合成

65* 神戸 大, 山口 宣朝, 山際 清史

グラフェン生成1P-22

錯体ナノ空間を利用したグラフェンナノリボンの精密合成

66* 北尾 岳史, マクレーン マイケル, 中田 和希, 植村 卓史
1P-23

Direct precipitation growth of multi-layer graphene using W capping layer-Dependence of growth atmosphere-67* 山田 純平, 上田 悠貴, 丸山 隆浩, 成塚 重弥

グラフェンの応用
1P-24

ナノグラフェン集合体におけるNOx吸着ダイナミクス

68* 日景 結理奈, 西嶌 里美, 高井 和之
1P-25

酸化グラフェンの化学構造と触媒活性との相関69* 鈴木 隆太郎, 井坂 琢也, 田嶋 健太郎, 中原 花菜, 松尾 吉晃, 赤井 伸行, 高井 和之

グラフェンの物性
1P-26

Investigation of surface potential variations of thermally reduced graphene oxide* K. Kanishka H. De Silva, Shuhei Ogawa, Pamarti Vishwanath, Masamichi Yoshimuravi

70

３月 １５日 （日）1P-27

グラフェンの電子輸送特性に対する水素分子の吸着効果

71* 重久 雄大, 小幡 吉徳, 石黒 康志, 高井 和之

原子層
1P-28

Multi-ferroic response of two-dimensional hexagonal materials

72* Fenda Rizky Pratama, M. Shoufie Ukhtary, Riichiro Saito
1P-29

Carrier-dependent photoluminescence properties of CVD-grown monolayer MoS2

73

* Kana Kojima, Hong En Lim, Yusuke Nakanishi, Takahiko Endo, Yutaka Maniwa,
Yasumitsu Miyata

ナノ炭素粒子
1P-30

ナノダイヤモンドの溶液からソフトゲルを経由した自己組織化

74* 田中 利彦, 三浦 康弘, 青山 哲也, 根本 雅哉, 安藤 柊介, 板橋 佑歩, 宮本 和範,
村中 厚哉, 内山 真伸, 大澤 映二

その他
1P-31

化学的手法により発生させた二原子炭素(C2)による炭素同素体の合成

75* 宮本 和範, 成田 将大, 増本 優衣, 橋新 崇広, 大澤 泰生, 木村 睦, 落合 正仁,
内山 真伸＞＞＞＞＞＞＞ 昼食 ( 12:15-13:30 ) ＜＜＜＜＜＜＜ポスターセッション ( 13:30-15:15 )13:30-14:00 若手奨励賞候補審査優先時間

特別講演 ( 15:15-15:45 )1S-1

ファンデルワールス界面の創発物性1* 中野 匡規

一般講演 ( 15:45-16:30 )グラフェン生成 ･ 原子層 ･ グラフェンの物性
1-7伝導ギャップ制御に向けたホモ接合グラフェンナノリボンの合成

23* 小倉 士忠, 金子 俊郎, 加藤 俊顕
1-8遷移金属酸化物ナノシート単層膜を用いたメタン酸化反応の電気的モニタリング

24* 野内 亮, 石原 良晃, 杉本 渉
1-9

Mechanical properties of 2D materials, scaling from monolayer to macroscale

25* Dai-Ming Tang, Xin Zhou, Fengchun Hsia, Yoshio Bando, Dmitri Golberg

特別講演 ( 16:30-17:00 )1S-2

導電性カーボンナノチューブコートPETテープに乗せた神経組織の高解像度電子顕微鏡
撮影とその解析法* 窪田 芳之vii

2

３月 １５日 （日）一般講演 ( 17:00-18:00 )内包ナノチューブ ・ 金属内包フラーレン ・ その他
1-10

Long Linear Carbon Chains inside CNT Formed by Electric Discharge of a SWCNT film

26

* 齋藤 弥八, 安坂 幸師, 石田 稔幸
1-11

Plasma Implantation of Lithium-Ion into Inner Space of C70: Synthesis andCharacterization of Lithium-Ion-Encapsulated C70 (Li+@C70)

27* Hiroshi Ueno, Kazuhiko Kawachi, Daiki Kitabatake, Keijiro Ohshimo, Hiroshi Okada,
Eunsang Kwon, Shinobu Aoyagi, Yasuhiko Kasama, Fuminori Misaizu
1-12

The Cage Dependence of Single Molecule Magnet Properties of Dy-dimetallofullerene
Anions28* 髙井 良也, 東中 隆二, 青木 勇二, 菊地 耕一, 阿知波 洋次, 兒玉 健
1-13

ナノ物質のための移動度・電荷・光測定システムの開発* 菅井 俊樹, 内山 史章, 大石 祐也, 宮本 莉央奈, 佐々木 諒, 仲安 貴紀, 小栗 奏太,
小野 智也＞＞＞＞＞＞＞ 休憩 ( 18:00-18:15 ) ＜＜＜＜＜＜＜チュートリアル ( 18:15-19:45 )ナノカーボン・原子層物質における光物性の基礎と応用* 松田 一成viii

29

３月 １６日 （月）特別講演
発表 ２５分 ・ 質疑応答 ５分
一般講演
発表 １０分 ・ 質疑応答 ５分
ポスタープレビュー
発表 １分 ・ 質疑応答 なし

特別講演 ( 9:00-9:30 ) 【CREST】
2S-1

High power factor, completely organic thermoelectric nanocomposites enabled by carbon
nanoparticles

3* Jaime C. Grunlan

一般講演 ( 9:30-10:15 ) 【CREST】
ナノチューブの物性 ・ 原子層 【CREST】
2-1

半導体型単層カーボンナノチューブの熱電特性における一次元性30

一ノ瀬 遥太, 上治 寛, 蓬田 陽平, * 柳 和宏
2-2Synthesis of Boron Nitride Nanotubes and MoS2@BNNTs Heteronanotubes

31* Ming Liu, Yongjia Zheng, Yang Qian, Rong Xiang, Taiki Inoue, Shohei Chiashi,
Esko I. Kauppinen, Shigeo Maruyama
2-3

Influence of interlayer stacking on gate-induced carrier accumulation in a van der Waals
heterostructure comprising MoS2 and WS2

32* Mina Maruyama, Susumu Okada＞＞＞＞＞＞＞ 休憩 ( 10:15-10:30 ) ＜＜＜＜＜＜＜特別講演 ( 10:30-11:00 )2S-2

燃料電池用窒素ドープカーボン触媒の活性点4* 中村 潤児

一般講演 ( 11:00-11:30 )原子層 ・ グラフェンの応用
2-4First-principles electronic-structure study of stabilities and electronic propertiesof trilayer h-BN33

* 芳賀 太史, 松浦 雄斗, 藤本 義隆, 斎藤 晋
2-5

グラフェン/Au電極への分子修飾の評価とプロトン透過能への影響

34* 福島 知宏, 駒井 貴羽, 長谷部 秀尭, 村越 敬

ポスタープレビュー ( 11:30-12:15 )若手奨励賞候補（☆） 若手奨励賞候補

2P-1

超音波照射による簡便で効果的な単層カーボンナノチューブの発光特性制御☆

* 紺野 優以, 西野 朱音, 山田 道夫, 前田 優, 奥平 早紀, 宮内 雄平, 松田 一成,
松井 淳, 三ツ石 方也, 鈴木 光明

2P-2

Stable MoO3 Doping of Carbon Nanotube Top Electrodes for Highly Efficient
Metal-Electrode-Free Perovskite Solar Cells☆

* Seungju Seo, Il Jeon, Esko I. Kauppinen, Yutaka Matsuo, Shigeo Maruyama

ix

76

77

３月 １６日 （月）2P-3☆

Macrocyclic bis(dipyrrinato) metal complex for single-walled carbon nanotube separation

2P-4

Influence of the carbon-rich domain in hexagonal boron nitride on transport propertiesof adjacent graphene☆

* 小野寺 桃子, 渡邊 賢司, 諌山 都子, 増渕 覚, 守谷 頼, 谷口 尚, 町田 友樹

2P-5

Dielectric screening effects on photoluminescence of carbon nanotubes on hexagonalboron nitride☆

* Nan Fang, Keigo Otsuka, Takashi Taniguchi, Kenji Watanabe, Kosuke Nagashio,
Yuichiro Kato

2P-6

Synthesis of 3D hybrid Structures composed of Single-walled CNTs and Mesopores Carbon
by Chemical Vapor Deposition☆

* Aliza Khaniya Sharma, Kamal P Sharma, Takahiro Saida, Shigeya Naritsuka,
Takahiro Maruyama

2P-7
☆

78

* Guoqing Cheng, Naoki Komatsu

電気・熱回路網解析によるCNT薄膜の熱電性能の理論設計

79

80

81

82

* 小林 遵栄, 藤崎 小太郎, 山本 貴博

ナノチューブの物性 【CREST】
2P-8

Evaluation of Thermal Transport in a Single-walled Carbon Nanotube Filmby Ionic-liquid Gating

83* Kan Ueji, Yuya Matsuoka, Takashi Yagi, Kengo Fukuhara, Yota Ichinose,
Akari Yoshida, Yohei Yomogida, Kazuhiro Yanagi
2P-9

Thermal stability of single-chirality-enriched carbon nanotube thin films

84* Akira Takakura, Taishi Nishihara, Kazunari Matsuda, Takeshi Tanaka,
Hiromichi Kataura, Yuhei Miyauchi
2P-10

Relationships between Seebeck coefficient and Conduction Directions in Aligned
Semiconducting Single-wall Carbon Nanotube Films

85* Kengo Fukuhara, Yota Ichinose, Kanako Horiuchi, Akari Yoshida, Yohei Yomogida,
Weilu Gao, Natsumi Komatsu, Junichiro Kono, Kazuhiro Yanagi

ナノチューブの応用 【CREST】
2P-11

カーボンナノチューブ繊維のマクロスケール四端子熱伝導測定

86

佐藤 彰斗, 足立 建人, * 児玉 高志

グラフェンの応用 【CREST】
2P-12

Bubble induced damage on graphene liquid cells during TEM observation87* 廣川 颯汰, 手嶋 秀彰, Pablo S. Fernandez, 吾郷 浩樹, 塘 陽子, Qin-Yi Li, 高橋 厚史

グラフェンの物性 【CREST】
2P-13

歪印加によるグラフェンのPFの向上

88* 鈴木 康平, 笹岡 健二, 山本 貴博

x

３月 １６日 （月）2P-14

端の欠陥によるグラフェンナノリボンのスピンフィルター効果

89* 安部 直椰, 笹岡 健二, 山本 貴博

原子層 【CREST】
2P-15

Anomalous electroluminescence from WS2/WSe2 in-plane heterostructures

90* Naoki Wada, Jiang Pu, Tomoyuki Yamada, Wenjin Zhang, Zheng Liu, Yusuke Nakanishi,
Yutaka Maniwa, Kazunari Matsuda, Yuhei Miyauchi, Taishi Takenobu, Yasumitsu Miyata

フラーレンの化学2P-16

C60赤外吸収の絶対強度と相対強度

91* 若林 知成, 百瀬 孝昌, ファハールト マリオ E.
2P-17

A one-step direct oxidation of alkoxy to ketone: oxidation of alkoxy indano[60]fullerenes
to [60]fullerene-fused ketones via weak copper oxidant

92* Yue Ma, Hao-Sheng Lin, Yun Yu, Shigeo Maruyama, Il Jeon, Yutaka Matsuo

金属内包フラーレン
2P-18

ESR study of La and Y hetero-dimetallofullerene anions

93* 前島 萌乃, 菊地 耕一, 阿知波 洋次, 兒玉 健
2P-19

-

-

ESR Study of two isomers of [Sc2C80] : [Sc2C80(1)] and [Sc2C80(2)]-94* 吉田 俊, 古川 貢, 菊地 耕一, 阿知波 洋次, 兒玉 健

ナノチューブの物性
2P-20

局所化学修飾単層カーボンナノチューブのドープ構造の違いに依存した発光ソルバトクロミズム挙動

95* 白木 智丈, 新留 嘉彬, 藤ヶ谷 剛彦

ナノチューブの応用
2P-21

PEN基板上のCNT薄膜電極を用いたＸ線の電気的検出96* 松田 裕之, 鈴木 慧, 石川 剛弘, 小西 輝昭, 濱野 毅, 大野 雄高, 平尾 敏雄, 石井 聡

ナノチューブの生成と精製
2P-22

Understanding and controlling the pyrolysis of C3H8 for uniform synthesisof vertically-aligned single-wall carbon nanotubes

97* MengJu Yang, Pengfei Chen, Rei Nakagawa, Hisashi Sugime, Hitoshi Mazaki,
Suguru Noda
2P-23

新しいホウ素原料を用いた化学気相成長法による窒化ホウ素ナノチューブの合成

98* 沢田 哲郎, 高橋 宏夢, 清 智弘, 安積 茉由, 大沢 利男, 杉目 恒志, 野田 優
2P-24

CNT分散剤フラビンの昇華性

99* 加藤 雄一, 小橋 和文, 山田 健郎, 畠 賢治
2P-25

CVD synthesis of sub-nanometer diameter single-walled CNTs

* Kamal Prasad Sharma, Daiki Yamamoto, Aliza Khaniya Sharma, Takahiro Maruyama

xi

100

３月 １６日 （月）グラフェン生成2P-26

a面サファイア上のグラフェンのCVD成長メカニズムの検討

101* 上田 悠貴, 山田 純平, 丸山 隆浩, 成塚 重弥

グラフェンの応用
2P-27

Heteroatom-doped Nanocarbons as Active Support for IrO2 as an OER Electrocatalyst

102* Prerna Joshi, Rohit Yadav, Masanori Hara, Masamichi Yoshimura

ナノ炭素粒子2P-28

溶液中のナノダイヤモンドとの相互作用その１：イオン

103* 根本 雅哉, 安藤 柊介, 板橋 佑歩, 田中 利彦, 三浦 康弘, 青山 哲也, 村中 厚哉,
内山 真伸, 大澤 映二
2P-29

溶液中のナノダイヤモンドとの相互作用その2：色素イオン104* 板橋 佑歩, 安藤 柊介, 根本 雅哉, 田中 利彦, 三浦 康弘, 青山 哲也, 村中 厚哉,
内山 真伸, 大澤 映二

バイオ
2P-30

Detection of odor molecules by transistor-type graphene biosensor* 本間 千柊, 野口 紘長, 磯林 厚伸, 杉崎 吉昭, 早水 裕平＞＞＞＞＞＞＞ 昼食 ( 12:15-13:30 ) ＜＜＜＜＜＜＜ポスターセッション ( 13:30-15:15 )13:30-14:00 若手奨励賞候補審査優先時間

大澤賞・飯島賞・若手奨励賞の授賞式 ( 15:15-16:00 )

xii

105

３月 １６日 （月）C60芳香族安定性予言50周年記念セッション ( 16:00-17:15 )2C-1

The beginning of nano-carbon era －Prediction and discovery of C60－

11* 阿知波 洋次
2C-2炭素クラスターC60

12* 斎藤 晋2C-3炭素のTEM観察：アモルファス炭素、フラーレンそしてカーボンナノチューブ

13* 飯島 澄男

祝辞紹介* 若林 知成＞＞＞＞＞＞＞ 休憩 ( 17:15-17:30 ) ＜＜＜＜＜＜＜C60芳香族安定性予言50周年記念セッション ( 17:30-18:45 )2C-4

サッカーボール分子C60の50年

14* 大澤 映二
2C-5

宇宙におけるフラーレンの起源を解明する ーフラーレンを有する惑星状星雲の物理的性質についてー

15* 大塚 雅昭, F.Kemper, J.Cami, E.Peeters, Fullerene PN consortium
2C-6

簡便・汎用合成が生み出す湾曲ナノカーボン分子* 磯部 寛之

xiii

16

３月 １７日 （火）特別講演
発表 ２５分 ・ 質疑応答 ５分
一般講演
発表 １０分 ・ 質疑応答 ５分
ポスタープレビュー
発表 １分 ・ 質疑応答 なし

特別講演 ( 9:00-9:30 ) 【CREST】
3S-1

Gating IR in Textiles

5* YuHuang Wang

一般講演 ( 9:30-10:15 ) 【CREST】
ナノチューブの応用 ・ ナノチューブの生成と精製 【CREST】
3-1

Carbon nanotube-based excitonic wavelength-selective absorber and emitter for solar
thermal energy harvesting35* Yuhei Miyauchi, Taishi Nishihara, Akira Takakura, Kazunari Matsuda, Takeshi Tanaka,
Hiromichi Kataura
3-2Machine-learned 100 %-yield carbon nanotube dissolution in arbitrary organic solvents36* 野々口 斐之, 宮尾 知幸, 後藤 千草, 村山 智子, 船津 公人, 河合 壯
3-3ゲル、SWCNTおよび界面活性剤間のマルチスケール疎水性相互作用：詳細議論

37

王 国偉, 田中 丈士, * 片浦 弘道＞＞＞＞＞＞＞ 休憩 ( 10:15-10:30 ) ＜＜＜＜＜＜＜特別講演 ( 10:30-11:00 )3S-2

Selective growth of single walled carbon nanotubes : thermodynamics versus kinetics

6* Christophe Bichara

一般講演 ( 11:00-11:30 )その他 ・ ナノチューブの物性
3-4WS2ナノチューブにおけるバルク光起電力効果

38* 張 奕勁, 井手上 敏也, 恩河 大, 秦 峰, 鈴木 龍二, Alla Zak, Reshef Tenne,
Jurgen Smet, 岩佐 義宏
3-5

Radiative quantum efficiency of bright excitons in carbon nanotubes

39* Hidenori Machiya, Akihiro Ishii, Yuichiro K. Kato

ポスタープレビュー ( 11:30-12:15 )若手奨励賞候補（☆） 若手奨励賞候補

3P-1

Highly Selective and Scalable Fullerene-Cation-Mediated Synthesis acessing
Cyclo[60]fullerenes with 5-Membered-Carbon-Ring and their Application to Perovskite
Solar Cells☆

* 林 昊升, 田 日, 丸山 茂夫, 松尾 豊

3P-2

Flattening of 2D materials encapsulated by hBN flakes☆

* Takato Hotta, Akihiro Ueda, Shohei Higuchi, Keiji Ueno, Kenji Watanabe,
Takashi Taniguchi, Ryo Kitaura

xiv

106

107

３月 １７日 （火）3P-3☆

SMART-EM法によるペプチド及びその凝集体解析のための修飾CNHの開発

108

3P-4
☆

周期構造修飾されたグラフェンの電子物性

3P-5☆

In-plane heterostructure of MoS2 polytypes

3P-6☆

その場観測により観測された単層WS2の高速成長

3P-7

単層CNT成長における添加ガスの効果の同位体ラベル分析☆

* 小矢野 文章, 山元 隼, 小林 明香里, 石丸 亮哉, 大塚 慶吾, 井ノ上 泰輝, 項 栄,
千足 昇平, 丸山 茂夫* 中室 貴幸, 孫 克己, Bode Jeffery W., 原野 幸治, 中村 栄一
109* 田口 裕太, 斎藤 晋
110

* Ruben Canton Vitoria, Ryo Kitaura
111* 亀山 智矢, 金子 俊郎, 加藤 俊顕
112

ナノチューブの物性 【CREST】
3P-8

Electronic property of CNT thin film under external electric field

113* 高 燕林, 岡田 晋
3P-9

金属型単層カーボンナノチューブ配列薄膜におけるホール効果と弱局在伝導114* 堀内 加奈子, Ryotaro Okada, Hideki Kawai, Yohei Yomogida, Natsumi Komatsu,
Weilu Gao, Junichiro Kono, Kazuhiro Yanagi

グラフェンの物性 【CREST】
3P-10

Influence of interlayer stacking arrangements on carrier accumulation in bilayer
graphene field effect transistors

115* Susumu Okada, Yanlin Gao, Mina Maruyama
3P-11

Study on effects of twist on phonon transport in graphene nanoribbons

116* Yukihiko Terada, Takuma Shiga

バイオ 【CREST】
3P-12

鉄イオンが媒介するカーボンナノチューブによる補酵素NADHの酸化反応

117* 平野 篤, 和田 百代, 田中 丈士, 片浦 弘道

その他 【CREST】
3P-13

超高速膜ろ過用の六方晶窒化ホウ素ナノシート

118* Rasel Das, Pablo Solís-Fernández, Hiroki Ago
3P-14

Mechanical and electronic properties of copolymers of centrohexaquinane andcyclooctatetraene

119* 藤井 康丸, 丸山 実那, 岡田 晋

金属内包フラーレン-

3P-15

Single molecule magnet properties of Tb-dimetallofullerene anions: [Tb2@C80(Ih)] and[Tb2@C78(D3h)]-* 山岸 主暉, 東中 隆二, 青木 勇二, 菊地 耕一, 阿知波 洋次, 兒玉 健

xv

120

３月 １７日 （火）3P-16

Attempt to produce Sm-dimetallofullerenes

121* 藤田 直也, 菊地 耕一, 阿知波 洋次, 兒玉 健

ナノ環境と安全評価
3P-17

In vivo evaluation of biodistribution, toxicity and clearance of single wall carbon
nanotubes depending on the dispersants122* Ying Xu, Minfang Zhang, Mei Yang, Masako Yudasaka, Toshiya Okazaki

ナノチューブの応用
3P-18

Importance of structural parameters of CNTs for the Pt electrochemical durability
in CNT based Pt electrocatalysts in PEMFCs

123* Don Terrence Dhammika Weerathunga, Tsuyohiko Fujigaya
3P-19

A semitransparent terahertz imager made from chemically doped semiconducting carbon
nanotube thin films

124* 大井 かなえ, 李 恒, 鈴木 大地, 河合 壯, 河野 行雄, 野々口 斐之
3P-20

Compact Wearable Foot Pressure Sensors from MWCNT Coated Cotton Fibers
for Human Activity and Sporting Performance Monitoring

125* Md. Abdul Momin, Mohammad Jellur Rahman, Tetsu Mieno

ナノチューブの生成と精製
3P-21

Activation of Alkane for CVD Growfh of Single-Wall Carbon Nanotubes

126* Pengfei Chen, Mengju Yang, Rei Nakagawa, Hisashi Sugime, Hitoshi Mazaki,
Suguru Noda
3P-22

石英ウールへの配向カーボンナノチューブの合成および形態評価

127* 山口 宣朝, 神戸 大, 山際 清史
3P-23

化学気相成長法による窒化ホウ素ナノチューブ合成における触媒と原料の独立制御

128* 高橋 宏夢, 沢田 哲郎, 清 智弘, 安積 茉由, 大沢 利男, 杉目 恒志, 野田 優
3P-24

Selective dispersion of semiconducting single-walled carbon nanotubes by using alkyl
cellulose129* 八木 智子, 河合 壯, 野々口 斐之

ナノワイヤー
3P-25

Scaling laws on enhancement of the electric field inside a hollow cylinder

130* Yuan Tian, Muhammad Shoufie Ukhtary, Riichiro Saito

グラフェンの応用
3P-26

酸化グラフェンPLの増強：ジオキサン分散状態でのUV照射

131* 金澤 克樹, 佐野 正人
3P-27

グラフェンと量子ドットとの界面における相互作用の影響* 井上 禅, 石黒 康志, Alexader Baranov, Igor Nabiev, 高井 和之

xvi

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３月 １７日 （火）

原子層
3P-28

First-principles calculation of exciton of transition metal dichalcogenide133* Pang Xiaoqi, Nguyen T. Hung, Riichiro Saito
3P-29

Theoretic Study on Raman Active Modes of SnS Thin Films

134* 米盛 樹生, Sudipta Dutta, 長汐 晃輔, 若林 克法
3P-30

表面修飾された基板上のMoS2の電気伝導における分子吸着効果

135* 皆川 勇気, 梅原 太一, 高井 和之

その他
3P-31

Thermal conductivity of low-cost thermoelectric Mg3Bi2

136* Nguyen T. Hung, Riichiro Saito＞＞＞＞＞＞＞ 昼食 ( 12:15-13:30 ) ＜＜＜＜＜＜＜ポスターセッション ( 13:30-15:15 )13:30-14:00 若手奨励賞候補審査優先時間

特別講演 ( 15:15-15:45 )3S-3
In situ Study of Catalysts for Single-Walled Carbon Nanotube Growth* Yan Li, Feng Yang

7

一般講演 ( 15:45-16:15 )ナノチューブの物性 ・ ナノホーン
3-6

Vapor-Phase Functionalization of Air-Suspended Single-Walled Carbon Nanotubes
Using an Aryl-Halide40* Daichi Kozawa, Xiaojian Wu, Akihiro Ishii, Jacob Fortner, Keigo Otsuka, Rong Xiang,
Taiki Inoue, Shigeo Maruyama, YuHuang Wang, Yuichiro K. Kato
3-7

化学修飾カーボンナノホーンを用いた反応中間体の捕捉と原子分解能電顕構造解析

41* 原野 幸治, Xing Junfei, Schweighauser Luca, 岡田 賢, 中村 栄一

特別講演 ( 16:15-16:45 )3S-4

電子顕微鏡を使った低次元材料のナノスケール光学及び振動吸収スペクトル計測

8* 千賀 亮典, 末永 和知, Thomas Pichler

一般講演 ( 16:45-17:30 )原子層
3-8Independent degrees of freedom in two-dimensional materials

42* Sake Wang, F. R. Pratama, M. Shoufie Ukhtary, Riichiro Saito
3-9

極性に依存したGaN表面上での遷移金属ダイカルコゲナイドの光学特性

43* 毛利 真一郎, 小路 悠馬, 篠北 啓介, 松田 一成, 荒木 努
3-10

TaP における異常な偏光ラマンスペクトル44* 齋藤 理一郎, Pang Xiaoqi, Wang Tong, Nguyen T. Hungxvii

March 15th, Sun.
Special Lecture: 25min (Presentation) + 5min (Discussion)
Invited Lecture: 10min (Presentation) + 5min (Discussion)
General Lecture: 10min (Presentation) + 5min (Discussion)
Poster Preview: 1min (Presentation)

Invited Lecture ( 9:30-9:45 )1I-1
FC-CVD synthesis of CNTs from methane for transparent conductor applications* Esko I. Kauppinen, Qiang Zhang, Datta Sukanta, Hua Jiang
General Lecture ( 9:45-10:30 )Formation and purification of nanotubes ・ Applications of nanotubes
One-pot Separation of Semiconducting Single-walled Carbon Nanotubes Based1-1
on Supramolecular Chemistry* Naotoshi Nakashima

9

17

1-2

Fast synthesis of vertically aligned CNTs array exceeding one-centimeter height* Shunsuke Sakurai, Takashi Tsuji, Maho Yamada, Kenji Hata, Don N. Futaba

18

1-3

Luminescence of CNTs by luciferin/luciferase reaction from firefly* Takeshi Tanaka, Mahoko Higuchi, Atsunori Hiratsuka, Hiromichi Kataura

19＞＞＞＞＞＞＞ Coffee Break ( 10:30-10:45 ) ＜＜＜＜＜＜＜General Lecture ( 10:45-11:30 )Applications of nanotubes
Selective Activation of Singlet/Triplet Reaction Paths Enabled
1-4
by Carbon-nanotube-mediated Energy Attenuation* Dongxin Liu, Dominik Lungerich, Satori Kowashi, Takayuki Nakamuro,
Kaoru Yamanouchi, Koji Harano, Eiichi Nakamura
1-5

1-6

Polyaromatic Anthracene Nano-tweezer on Semiconducting Carbon Nanotubes
for Growth and Bridging of Perovskite Crystal Grains in Perovskite Solar Cells* Hao-Sheng Lin, Shuhei Okawa, IL Jeon, Yutaka Matsuo, Shigeo Maruyama
Optimization of the Alignment Relay Technique for the Controlled Orientationand Selection of Single-Walled Carbon Nanotubes* Monika Snowdon, Derek Schipper, Dai-ming Tang

Poster Preview ( 11:30-12:15 ) （☆）Candidates for the Young Scientist Poster Award
Candidates for the Young Scientist Poster Award
Organic field effect transistor of C70 single crystals with rod shape
1P-1☆
* Ryohei Yamamoto, Tadahiko Hirai, Nobuyuki Aoki, Masaru Tachibana

xviii

20

21

22

45

March 15th, Sun.

1P-2☆

Alteration of Fermi-Level of Single-Wall Carbon Nanotubes via Protein Adsorption
Observed by Ultrafast Spectroscopy* Tomohito Nakayama, Takeshi Tanaka, Atsushi Hirano, Muneaki Hase☆

Mechanical properties and morphology of polypropylene/ethylene-1-butene
copolymer rubber/CNT composites* Yoshimi Muraoka, Kenzo Fukumori

1P-4☆

Understanding the Effect of Sulfur on the Synthesis of Carbon Nanotubes* Rei Nakagawa, Michiko Edo, Hisashi Sugime, Suguru Noda

1P-3

1P-5
☆
1P-6
☆

1P-7
☆

Evaluation of various nitrogen-doping in graphene on the performance
as a supercapacitor electrode* Rohit Yadav, Prerna Joshi, Masanori Hara, Masamichi Yoshimura

47

48

49

Gene expression analysis of macrophages on carbon nanohorn coated titanium* Sadahito Kimura, Eri Hirata, Sari Takada, Masatoshi Sakairi,
Masako Yudasaka, Atsuro Yokoyama

50

Unidirectional bright exciton transport in a WS2xSe(2-2x) alloy monolayer* Masafumi Shimasaki, Taishi Nishihara, Naoki Wada, Zheng Liu, Kana Kojima,
Keisuke Shinokita, Kazunari Matsuda, Yasumitsu Miyata, Yuhei Miyauchi

51

Properties of nanotubes 【CREST】
1P-8
Electronic structures of bundles of molybdenum disulfide nanotubes* Kaoru Hisama, Mina Maruyama, Susumu Okada, Shohei Chiashi,
Shigeo Maruyama
1P-9

46

Rayleigh scattering measurement of suspended SWCNTs coaxially wrappedwith BNNTs* Satoshi Yotsumoto, Hayato Arai, Yongjia Zheng, Taiki Inoue, Rong Xiang,
Shigeo Maruyama, Shohei Chiashi

52

53

1P-10

Optical properties of inorganic nanotubes with different diameters* Yohei Yomogida, Yasumitsu Miyata, Kazuhiro Yanagi

54

1P-11

Chemical vapor deposition of one-dimensional heterostructures* Yongjia Zheng, Yang Qian, Ming Liu, Akinito Kumamoto, Yuichi Ikuhara,
Esko I. Kauppinen, Shohei Chiashi, Taiki Inoue, Rong Xiang, Shigeo Maruyama

55

1P-12

Synthesis and Raman scattering spectroscopy of gas-flow oriented
single-walled carbon nanotubes on hexagonal boron-nitride* Shu Sato, Satoshi Yotsumoto, Masanori Bamba, Taiki Inoue,
Shigeo Maruyama, Shohei Chiashi

xix

56

March 15th, Sun.

1P-13

In-Plane Thermal Conductance of Thin Films Composed of Coaxially CombinedSingle-Walled Carbon Nanotubes and Boron Nitride Nanotubes* Pengyingkai Wang, Yongjia Zheng, Taiki Inoue, Rong Xiang, Ahmed Shawky,
Makoto Watanabe, Anton Anisimov, Esko I. Kauppinen, Shohei Chiashi,
Shigeo Maruyama

Applications of nanotubes 【CREST】
Fabrication of ribbon-like films with highly oriented carbon nanotubes using
1P-14
a robotic dispenser* Manish Pandey, Ryo Abe, Naofumi Okamoto, Yuki Sekimoto,
Masakazu Nakamura
Chemistry of fullerenes
Phosphorescence of polyynes: A key probe for the detection of a new series of laser
1P-15
ablated polyyne derivatives* Tomonari Wakabayashi, Nozomu Kitamura, Ayato Osawa, Daiki Okada,
Hal Suzuki, Yusuke Morisawa, Miho Hatanaka
1P-16

CuCl-Mediated Reaction of C60 with Propargylic Phosphate* Asumi Ishitsuka, Yutaka Maeda, Michio Yamada

Applications of fullerenes
Catalytic activity for the reduction of 4-nitrophenol using on gadolinium oxide
1P-17nanoparticle-[C60]fullerene nanowhisker composites* Jeong Won Ko, Sugyeong Jeon, Weon Bae Ko
Endohedral metallofullerenes
Reactions of S-Heterocyclic Carbenes with Fullerenes: Preparation and
1P-18
Characterization of Dithiomethano-derivatives* Yuta Maeda, Shinji Kanzawa, Masahiro Kako, Michio Yamada, Yutaka Maeda,
Makoto Furukawa, Takeshi Akasaka

57

58

59

60

61

62

Applications of nanotubes
1P-19 Research of Fracture Behavior of CNT/HDPE Composites via Melt Blending* Koichi Utsugi, Nao Otsuki, Masaru Sekido

63

Formation and purification of nanotubes
Preferential stability of carbon nanotubes with sub-nm diameter under linearly
1P-20
polarized laser irradiation: An ab initio TDDFT study* Yoshiyuki Miyamoto

64

1P-21

Synthesis of carbon nanotubes on nanozirconia-dispersed carbon paper* Dai Goudo, Nobutomo Yamaguchi, Kiyofumi Yamagiwa

xx65March 15th, Sun.

Graphene synthesis
Scalable Synthesis of Atomically Precise Graphene Nanoribbons
1P-22
in Metal-Organic Framework* Takashi Kitao, Michael MacLean, Kazuki Nakata, Takashi Uemura
1P-23

Direct precipitation growth of multi-layer graphene using W capping layer-Dependence of growth atmosphere* Jumpei Yamada, Yuki Ueda, Takahiro Maruyama, Shigeya Naritsuka

Applications of graphene
1P-24 NOx adsorption dynamics on Nanographene assembly system* Yurina Hikage, Satomi Nishijima, Kazuyuki Takai
1P-25

Correlation between chemical structure and catalytic activity of graphene oxide* Ryutaro Suzuki, Takuya Isaka, Kentaro Tajima, Kana Nakahara,
Yoshiaki Matsuo, Nobuyuki Akai, Kazuyuki Takai

Properties of graphene
1P-26 Investigation of surface potential variations of thermally reduced graphene oxide* K. Kanishka H. De Silva, Shuhei Ogawa, Pamarti Vishwanath,
Masamichi Yoshimura
1P-27

Adsorption effects of molecular Hydrogen on the electronic transport propertiesof Graphene* Yudai Shigehisa, Yoshinori Obata, Yasushi Ishiguro, Kazuyuki Takai

Atomic Layers
1P-28 Multi-ferroic response of two-dimensional hexagonal materials* Fenda Rizky Pratama, M. Shoufie Ukhtary, Riichiro Saito
1P-29

Carrier-dependent photoluminescence properties of CVD-grown monolayer MoS2
* Kana Kojima, Hong En Lim, Yusuke Nakanishi, Takahiko Endo,
Yutaka Maniwa, Yasumitsu Miyata

Carbon nanoparticles
1P-30 Self-Assembly of Nanodiamonds through Soft Gel from their Solutions* Toshihiko Tanaka, Yasuhiro F. Miura, Tetsuya Aoyama, Masaya Nemoto,Shusuke Ando, Yuho Itabashi, Kazunori Miyamoto, Atsuya Muranaka,
Masanobu Uchiyama, Eiji Osawa
Other topics
Chemically synthesized ground state diatomic carbon (C2) serves as an origin
1P-31
of carbon allotropes* Kazunori Miyamoto, Shodai Narita, Yui Masumoto, Takahiro Hashishin,
Taisei Osawa, Mutsumi Kimura, Masahito Ochiai, Masanobu Uchiyama
xxi

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67

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69

70

71

72

73

74

75

March 15th, Sun.

＞＞＞＞＞＞＞ Lunch Time ( 12:15-13:30 ) ＜＜＜＜＜＜＜Poster Session ( 13:30-15:15 )During 13:30-14:00, please give priority to selection of candidates for Young Scientist Poster Award

Special Lecture ( 15:15-15:45 )1S-1
Emergent phenomena at van der Waals interfaces* Masaki Nakano
General Lecture ( 15:45-16:30 )Graphene synthesis ・ Atomic Layers ・ Properties of graphene
1-7Fabrication of graphene nanoribbon homojunction for transport gap control* Noritada Ogura, Toshiro Kaneko, Toshiaki Kato
1-8

1-9

Electrical monitoring of methane oxidation reaction using monolayered filmsof transition-metal oxide nanosheets* Ryo Nouchi, Yoshiaki Ishihara, Wataru Sugimoto
Mechanical properties of 2D materials, scaling from monolayer to macroscale* Dai-Ming Tang, Xin Zhou, Fengchun Hsia, Yoshio Bando, Dmitri Golberg

Special Lecture ( 16:30-17:00 )High resolution electron micrographs of serial brain tissue sections on conductive
1S-2
carbon nanotube coated PET tape and neural microcircuit analysis* Yoshiyuki Kubota
General Lecture ( 17:00-18:00 )Endohedral nanotubes ・ Endohedral metallofullerenes ・ Other topics
Long Linear Carbon Chains inside CNT Formed by Electric Discharge
1-10
of a SWCNT film
* Yahachi Saito, Koji Asaka, Toshiyuki Ishida
1-11

1-12

Plasma Implantation of Lithium-Ion into Inner Space of C70: Synthesis andCharacterization of Lithium-Ion-Encapsulated C70 (Li+@C70)* Hiroshi Ueno, Kazuhiko Kawachi, Daiki Kitabatake, Keijiro Ohshimo,
Hiroshi Okada, Eunsang Kwon, Shinobu Aoyagi, Yasuhiko Kasama,
Fuminori Misaizu

The Cage Dependence of Single Molecule Magnet Properties
of Dy-dimetallofullerene Anions* Ryoya Takai, Ryuji Higashinaka, Yuji Aoki, Koichi Kikuchi, Yohji Achiba,
Takeshi Kodama

xxii

1

23

24

25

2

26

27

28

March 15th, Sun.

1-13

Development of Mobility, Charge and Optical Measurement System
for Nanomaterials* Toshiki Sugai, Fumiaki Uchiyama, Yuya Ooishi, Reona Miyamoto, Ryo Sasaki,
Takanori Nakayasu, Kanata Oguri, Tomoya Ono＞＞＞＞＞＞＞ Coffee Break ( 18:00-18:15 ) ＜＜＜＜＜＜＜Tutorial ( 18:15-19:45 )Fundamental and application of optical physics in nano-carbon andatomically thin materials* Kazunari Matsuda

xxiii

29

March 16th, Mon.
Special Lecture: 25min (Presentation) + 5min (Discussion)
General Lecture: 10min (Presentation) + 5min (Discussion)
Poster Preview: 1min (Presentation)

Special Lecture ( 9:00-9:30 ) 【CREST】
High power factor, completely organic thermoelectric nanocomposites enabled
2S-1
by carbon nanoparticles* Jaime C. Grunlan
General Lecture ( 9:30-10:15 ) 【CREST】
Properties of nanotubes ・ Atomic Layers 【CREST】
One dimensional characteristics in thermoelectric properties of semiconducting
2-1
single walled carbon nanotubes
Yota Ichinose, Kan Ueji, Yohei Yomogida, * Kazuhiro Yanagi
2-2

2-3

Synthesis of Boron Nitride Nanotubes and MoS2@BNNTs Heteronanotubes* Ming Liu, Yongjia Zheng, Yang Qian, Rong Xiang, Taiki Inoue, Shohei Chiashi,
Esko I. Kauppinen, Shigeo Maruyama
Influence of interlayer stacking on gate-induced carrier accumulation
in a van der Waals heterostructure comprising MoS2 and WS2* Mina Maruyama, Susumu Okada

3

30

31

32

＞＞＞＞＞＞＞ Coffee Break ( 10:15-10:30 ) ＜＜＜＜＜＜＜Special Lecture ( 10:30-11:00 )2S-2
Active site of nitrogen-doped carbon catalysts for fuel cell
* Junji Nakamura
General Lecture ( 11:00-11:30 )Atomic Layers ・ Applications of graphene
First-principles electronic-structure study of stabilities and electronic properties
2-4of trilayer h-BN
* Taishi Haga, Yuuto Matsuura, Yoshitaka Fujimoto, Susumu Saito
2-5

Molecular modification of graphene/Au electrode for controlled proton permeability* Tomohiro Fukushima, Takaha Komai, Hidetaka Hasebe, Kei Murakoshi

Poster Preview ( 11:30-12:15 ) （☆）Candidates for the Young Scientist Poster Award
Candidates for the Young Scientist Poster Award
Simple and Effective Method to Control Photoluminescence Properties
2P-1
of Single-walled Carbon Nanotubes by Ultrasonic Irradiation* Yui Konno, Akane Nishino, Michio Yamada, Yutaka Maeda, Saki Okudaira,☆
Yuhei Miyauchi, Kazunari Matsuda, Jun Matsui, Masaya Mitsuishi, Mitsuaki Suzuki

xxiv

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33

34

76

March 16th, Mon.

2P-2
☆
2P-3
☆
2P-4
☆

2P-5
☆

2P-6
☆

2P-7
☆

Stable MoO3 Doping of Carbon Nanotube Top Electrodes for Highly Efficient
Metal-Electrode-Free Perovskite Solar Cells* Seungju Seo, Il Jeon, Esko I. Kauppinen, Yutaka Matsuo, Shigeo Maruyama
Macrocyclic bis(dipyrrinato) metal complex for single-walled carbon nanotube
separation* Guoqing Cheng, Naoki Komatsu
Influence of the carbon-rich domain in hexagonal boron nitride on transport
properties of adjacent graphene* Momoko Onodera, Kenji Watanabe, Miyako Isayama, Satoru Masubuchi,
Rai Moriya, Takashi Taniguchi, Tomoki Machida
Dielectric screening effects on photoluminescence of carbon nanotubes
on hexagonal boron nitride* Nan Fang, Keigo Otsuka, Takashi Taniguchi, Kenji Watanabe, Kosuke Nagashio,
Yuichiro Kato
Synthesis of 3D hybrid Structures composed of Single-walled CNTs and Mesopores
Carbon by Chemical Vapor Deposition* Aliza Khaniya Sharma, Kamal P Sharma, Takahiro Saida, Shigeya Naritsuka,
Takahiro Maruyama
Theoretical Design of Thermoelectric Performance of Carbon Nanotube Thin Films
based on Electrical and Thermal Circuit Network Analysis* Junei Kobayashi, Kotaro Fujisaki, Takahiro Yamamoto

Properties of nanotubes 【CREST】
Evaluation of Thermal Transport in a Single-walled Carbon Nanotube Film
2P-8
by Ionic-liquid Gating* Kan Ueji, Yuya Matsuoka, Takashi Yagi, Kengo Fukuhara, Yota Ichinose,
Akari Yoshida, Yohei Yomogida, Kazuhiro Yanagi
2P-9

2P-10

Thermal stability of single-chirality-enriched carbon nanotube thin films* Akira Takakura, Taishi Nishihara, Kazunari Matsuda, Takeshi Tanaka,
Hiromichi Kataura, Yuhei Miyauchi
Relationships between Seebeck coefficient and Conduction Directions in Aligned
Semiconducting Single-wall Carbon Nanotube Films* Kengo Fukuhara, Yota Ichinose, Kanako Horiuchi, Akari Yoshida,
Yohei Yomogida, Weilu Gao, Natsumi Komatsu, Junichiro Kono, Kazuhiro Yanagi

xxv

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82

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84

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March 16th, Mon.

Applications of nanotubes 【CREST】
Macroscopic four probe thermal and thermoelectric measurement of carbon
2P-11
nanotube fibers
Akito Sato, Kento Adachi, * Takashi Kodama
Applications of graphene 【CREST】
2P-12 Bubble induced damage on graphene liquid cells during TEM observation* Sota Hirokawa, Hideaki Teshima, Pablo S. Fernandez, Hiroki Ago, Yoko Tomo,
Qin-Yi Li, Koji Takahashi
Properties of graphene 【CREST】
Strain-Induced Enhancement of Thermoelectric Power Factor of Graphene* Kohei Suzuki, Kenji Sasaoka, Takahiro Yamamoto

2P-13

2P-14

Spin-Filter Effect of Zigzag Graphene Nanoribbons with Egde Defects* Naoya Abe, Kenji Sasaoka, Takahiro Yamamoto

Atomic Layers 【CREST】
2P-15 Anomalous electroluminescence from WS2/WSe2 in-plane heterostructures* Naoki Wada, Jiang Pu, Tomoyuki Yamada, Wenjin Zhang, Zheng Liu,
Yusuke Nakanishi, Yutaka Maniwa, Kazunari Matsuda, Yuhei Miyauchi,
Taishi Takenobu, Yasumitsu Miyata
Chemistry of fullerenes
2P-16 Absolute and relative intensity of the C60 IR absorption* Tomonari Wakabayashi, Takamasa Momose, Mario E. Fajardo
2P-17

A one-step direct oxidation of alkoxy to ketone: oxidation of alkoxy
indano[60]fullerenes to [60]fullerene-fused ketones via weak copper oxidant* Yue Ma, Hao-Sheng Lin, Yun Yu, Shigeo Maruyama, Il Jeon, Yutaka Matsuo

Endohedral metallofullerenes
2P-18 ESR study of La and Y hetero-dimetallofullerene anions* Moeno Maejima, Koichi Kikuchi, Yohji Achiba, Takeshi Kodama
2P-19

ESR Study of two isomers of [Sc2C80]-: [Sc2C80(1)]- and [Sc2C80(2)]* Shun Yoshida, Ko Furukawa, Koichi Kikuchi, Yohji Achiba, Takeshi Kodama

Properties of nanotubes
Doped-site structure dependent energy shifts of photoluminescence from locally2P-20
functionalized single-walled carbon nanotubes in organic solvent environments* Tomohiro Shiraki, Yoshiaki Niidome, Tsuyohiko Fujigaya

xxvi

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March 16th, Mon.

Applications of nanotubes
Electrical detection of X-ray by using coplanar CNT thin-film electrodes on PEN
2P-21
substrate* Hiroyuki Matsuda, Satoru Suzuki, Takahiro Ishikawa, Teruaki Konishi,
Tsuyoshi Hamano, Yutaka Ohno, Toshio Hirao, Satoshi Ishii
Formation and purification of nanotubes
Understanding and controlling the pyrolysis of C3H8 for uniform synthesis
2P-22
of vertically-aligned single-wall carbon nanotubes* MengJu Yang, Pengfei Chen, Rei Nakagawa, Hisashi Sugime, Hitoshi Mazaki,
Suguru Noda
2P-23

2P-24

2P-25

Synthesis of boron nitride nanotube by chemical vapor deposition using new boron
source* Tetsuro Sawada, Hiromu Takahashi, Tomohiro Sei, Mayu Asaka, Toshio Osawa,
Hisashi Sugime, Suguru Noda
Sublimation property of a flavin compound which is a surfactant for carbon
nanotube dispersion* Yuichi Kato, Kazufumi Kobashi, Takeo Yamada, Kenji Hata
CVD synthesis of sub-nanometer diameter single-walled CNTs
* Kamal Prasad Sharma, Daiki Yamamoto, Aliza Khaniya Sharma,
Takahiro Maruyama

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2P-26

Graphene synthesis
Study of CVD growth mechanism of graphene on a-plane sapphire* Yuki Ueda, Jumpei Yamada, Takahiro Maruyama, Shigeya Naritsuka

101

Applications of graphene
2P-27 Heteroatom-doped Nanocarbons as Active Support for IrO2 as an OER Electrocatalyst* Prerna Joshi, Rohit Yadav, Masanori Hara, Masamichi Yoshimura

102

Carbon nanoparticles
2P-28 Interactions of Nanodiamonds #1: with Ions in their Solutions* Masaya Nemoto, Shusuke Ando, Yuho Itabashi, Toshihiko Tanaka,
Yasuhiro F. Miura, Tetsuya Aoyama, Atsuya Muranaka, Masanobu Uchiyama,
Eiji Osawa
2P-29

Interactions of Nanodiamonds #2: with Dye Ions in their Solutions* Yuho Itabashi, Shusuke Ando, Masaya Nemoto, Toshihiko Tanaka,
Yasuhiro F. Miura, Tetsuya Aoyama, Atsuya Muranaka, Masanobu Uchiyama,
Eiji Osawa

xxvii

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March 16th, Mon.

Bio
2P-30

Detection of odor molecules by transistor-type graphene biosensor* Chishu Homma, Hironaga Noguchi, Atsunobu Isobayashi, Yoshiaki Sugizaki, Yuhei
Hayamizu

105＞＞＞＞＞＞＞ Lunch Time ( 12:15-13:30 ) ＜＜＜＜＜＜＜Poster Session ( 13:30-15:15 )During 13:30-14:00, please give priority to selection of candidates for Young Scientist Poster Award

Awards Ceremony ( 15:15-16:00 )The 50 th Anniversary of the Prediction of Aromatic Stability of C6060
Commemorative Session ( 16:00-17:15 )The beginning of nano-carbon era －Prediction and discovery of C60－
2C-1
* Yohji Achiba

11

2C-2

C60 as a carbon cluster* Susumu Saito

12

2C-3

TEM Observations of Carbon: Amorphous, Fullerenes and Carbon nanotubes* Sumio Iijima

13

Celebration Messages* Tomonari Wakabayashi＞＞＞＞＞＞＞ Coffee Break ( 17:15-17:30 ) ＜＜＜＜＜＜＜The 50 th Anniversary of the Prediction of Aromatic Stability of C6060
Commemorative Session ( 17:30-18:45 )The 50 years of a soccer-ball molecule C60
2C-4* Eiji Osawa
2C-5

2C-6

Unveiling the origin of cosmic fullerenes through investigations into physicalproperties of fullerene-containing planetary nebulae* Masaaki Otsuka, F. Kemper, J. Cami, E. Peeters, Fullerene PN consortium
Curved nanocarbon molecules from concise and versatile synthesis* Hiroyuki Isobe

xxviii14

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March 17th, Tue.
Special Lecture: 25min (Presentation) + 5min (Discussion)
General Lecture: 10min (Presentation) + 5min (Discussion)
Poster Preview: 1min (Presentation)

Special Lecture ( 9:00-9:30 ) 【CREST】
3S-1
Gating IR in Textiles* YuHuang Wang

5

General Lecture ( 9:30-10:15 ) 【CREST】
Applications of nanotubes ・ Formation and purification of nanotubes 【CREST】
Carbon nanotube-based excitonic wavelength-selective absorber and emitter
3-1
for solar thermal energy harvesting* Yuhei Miyauchi, Taishi Nishihara, Akira Takakura, Kazunari Matsuda,
Takeshi Tanaka, Hiromichi Kataura

35

3-2

3-3

Machine-learned 100 %-yield carbon nanotube dissolution in arbitrary organic
solvents* Yoshiyuki Nonoguchi, Tomoyuki Miyao, Chigusa Goto, Tomoko Murayama,
Kimito Funatsu, Tsuyoshi Kawai
Multiscale hydrophobic interactions between gel, SWCNTs, and surfactants:
detailed discussions
Guowei Wang, Takeshi Tanaka, * Hiromichi Kataura

3637＞＞＞＞＞＞＞ Coffee Break ( 10:15-10:30 ) ＜＜＜＜＜＜＜Special Lecture ( 10:30-11:00 )3S-2
Selective growth of single walled carbon nanotubes : thermodynamics versus kinetics* Christophe Bichara

6

General Lecture ( 11:00-11:30 )Other topics ・ Properties of nanotubes
3-4
Enhanced intrinsic photovoltaic effect in tungsten disulfide nanotubes* Yijin Zhang, Toshiya Ideue, Masaru Onga, Feng Qin, Ryuji Suzuki, Alla Zak,
Reshef Tenne, Jurgen Smet, Yoshihiro Iwasa

38

3-5

Radiative quantum efficiency of bright excitons in carbon nanotubes* Hidenori Machiya, Akihiro Ishii, Yuichiro K. Kato

Poster Preview ( 11:30-12:15 ) （☆）Candidates for the Young Scientist Poster Award
Candidates for the Young Scientist Poster Award
Highly Selective and Scalable Fullerene-Cation-Mediated Synthesis acessing
3P-1
Cyclo[60]fullerenes with 5-Membered-Carbon-Ring and their Application to
Perovskite Solar Cells☆
* Hao-Sheng Lin, IL Jeon, Shigeo Maruyama, Yutaka Matsuo

xxix

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March 17th, Tue.

3P-2☆

Flattening of 2D materials encapsulated by hBN flakes* Takato Hotta, Akihiro Ueda, Shohei Higuchi, Keiji Ueno, Kenji Watanabe,
Takashi Taniguchi, Ryo Kitaura

107☆

Development of Chemical CNH Fishhok for Analyzing Peptide and Its Assemblies
by SMART-EM* Takayuki Nakamuro, Keyi Sun, Jeffery W. Bode, Koji Harano, Eiichi Nakamura

3P-4☆

Electrical properties of periodically modified graphene* Yuta Taguchi, Susumu Saito

109

3P-5
☆

In-plane heterostructure of MoS2 polytypes* Ruben Canton Vitoria, Ryo Kitaura

110

3P-6
☆

Ultra fast growth of monolayer WS2 measured by in-situ monitoring* Tomoya Kameyama, Toshiro Kaneko, Toshiaki Kato

111

3P-3

3P-7
☆

Isotope Labelling Analysis of Additive Gas Effects on Single-Walled
Carbon Nanotube Growth* Bunsho Koyano, Shun Yamamoto, Akari Kobayashi, Ryoya Ishimaru,
Keigo Otsuka, Taiki Inoue, Rong Xiang, Shohei Chiashi, Shigeo Maruyama

Properties of nanotubes 【CREST】
3P-8
Electronic property of CNT thin film under external electric field* Yanlin Gao, Susumu Okada
3P-9

Hall Effect and weak-localization conduction in aligned metallic single-walledcarbon nanotube thin films* Kanako Horiuchi, Ryotaro Okada, Hideki Kawai, Yohei Yomogida,
Natsumi Komatsu, Weilu Gao, Junichiro Kono, Kazuhiro Yanagi

Properties of graphene 【CREST】
Influence of interlayer stacking arrangements on carrier accumulation in bilayer
3P-10
graphene field effect transistors* Susumu Okada, Yanlin Gao, Mina Maruyama
3P-11

Study on effects of twist on phonon transport in graphene nanoribbons* Yukihiko Terada, Takuma Shiga

Bio 【CREST】
3P-12 Iron ion-mediated oxidation of coenzyme NADH by carbon nanotubes* Atsushi Hirano, Momoyo Wada, Takeshi Tanaka, Hiromichi Kataura

xxx

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March 17th, Tue.

Other topics 【CREST】
Hexagonal boron nitride nanosheets for ultrafast membrane filtration* Rasel Das, Pablo Solís-Fernández, Hiroki Ago

3P-13

3P-14

Mechanical and electronic properties of copolymers of centrohexaquinane andcyclooctatetraene* Yasumaru Fujii, Mina Maruyama, Susumu Okada

Endohedral metallofullerenes
Single molecule magnet properties of Tb-dimetallofullerene anions: [Tb2@C80(Ih)]-

118

119

3P-15

and [Tb2@C78(D3h)]* Kazuki Yamagishi, Ryuji Higashinaka, Yuji Aoki, Koichi Kikuchi, Yohji Achiba,
Takeshi Kodama

120

3P-16

Attempt to produce Sm-dimetallofullerenes* Naoya Fujita, Koichi Kikuchi, Yohji Achiba, Takeshi Kodama

121

Environmental/Safety characterization of nanomaterials
In vivo evaluation of biodistribution, toxicity and clearance of single wall carbon
3P-17
nanotubes depending on the dispersants* Ying Xu, Minfang Zhang, Mei Yang, Masako Yudasaka, Toshiya Okazaki

122

Applications of nanotubes
Importance of structural parameters of CNTs for the Pt electrochemical durability
3P-18
in CNT based Pt electrocatalysts in PEMFCs* Don Terrence Dhammika Weerathunga, Tsuyohiko Fujigaya

123

3P-19

3P-20

A semitransparent terahertz imager made from chemically doped semiconducting
carbon nanotube thin films* Kanae Oi, Kou Li, Daichi Suzuki, Tsuyoshi Kawai, Yukio Kawano,
Yoshiyuki Nonoguchi
Compact Wearable Foot Pressure Sensors from MWCNT Coated Cotton Fibers
for Human Activity and Sporting Performance Monitoring* Md. Abdul Momin, Mohammad Jellur Rahman, Tetsu Mieno

Formation and purification of nanotubes
3P-21 Activation of Alkane for CVD Growth of Single-Wall Carbon Nanotubes* Pengfei Chen, Mengju Yang, Rei Nakagawa, Hisashi Sugime, Hitoshi Mazaki,
Suguru Noda
3P-22

Synthesis of aligned carbon nanotube arrays on quartz wool and its morphologicalcharacterization* Nobutomo Yamaguchi, Dai Goudo, Kiyofumi Yamagiwa

xxxi

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March 17th, Tue.

3P-23

3P-24

Separate control of catalyst and source gases in synthesis of boron nitride nanotubes
by chemical vapor deposition* Hiromu Takahashi, Tetsuro Sawada, Tomohiro Sei, Mayu Asaka, Toshio Osawa,
Hisashi Sugime, Suguru Noda
Selective dispersion of semiconducting single-walled carbon nanotubes
by using alkyl cellulose* Tomoko Yagi, Tsuyoshi Kawai, Yoshiyuki Nonoguchi

128

129

Nanowires
3P-25 Scaling laws on enhancement of the electric field inside a hollow cylinder* Yuan Tian, Muhammad Shoufie Ukhtary, Riichiro Saito

130

Applications of graphene
3P-26 Photoluminescence of Graphene Oxide Enhanced by UV-radiation in Dioxane* Katsuki Kanazawa, Masahito Sano

131

3P-27

Effects of interactions at the interface between graphene and quantum dots on theirelectronic properties* Zen Inoue, Yasushi Ishiguro, Alexader Baranov, Igor Nabiev, Kazuyuki Takai

Atomic Layers
First-principles calculation of exciton of transition metal dichalcogenide* Pang Xiaoqi, Nguyen T. Hung, Riichiro Saito

3P-28

3P-29

3P-30

Theoretic Study on Raman Active Modes of SnS Thin Films* Itsuki Yonemori, Sudipta Dutta, Kosuke Nagashio, Katsunori Wakabayashi
Molecular adsorption effects on the electrical conduction of MoS2
on surface-modified substrates* Yuki Minakawa, Taichi Umehara, Kazuyuki Takai

Other topics
3P-31 Thermal conductivity of low-cost thermoelectric Mg3Bi2* Nguyen T. Hung, Riichiro Saito

132

133

134

135

136

＞＞＞＞＞＞＞ Lunch Time ( 12:15-13:30 ) ＜＜＜＜＜＜＜Poster Session ( 13:30-15:15 )During 13:30-14:00, please give priority to selection of candidates for Young Scientist Poster Award

Special Lecture ( 15:15-15:45 )3S-3
In situ Study of Catalysts for Single-Walled Carbon Nanotube Growth* Yan Li, Feng Yang
xxxii

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March 17th, Tue.

General Lecture ( 15:45-16:15 )Properties of nanotubes ・ Nanohorns
Vapor-Phase Functionalization of Air-Suspended Single-Walled Carbon Nanotubes
3-6
Using an Aryl-Halide* Daichi Kozawa, Xiaojian Wu, Akihiro Ishii, Jacob Fortner, Keigo Otsuka,
Rong Xiang, Taiki Inoue, Shigeo Maruyama, YuHuang Wang, Yuichiro K. Kato
3-7

Atomistic Structural Analysis of Reaction Intermediates Captured on Functionalized
Carbon Nanohorns* Koji Harano, Junfei Xing, Luca Schweighauser, Satoshi Okada, Eiichi Nakamura

Special Lecture ( 16:15-16:45 )Nanoscale optical and vibrational spectroscopy of low-dimensional materials
3S-4
in electron microscope* Ryosuke Senga, Kazu Suenaga, Thomas Pichler
General Lecture ( 16:45-17:30 )Atomic Layers
3-8
Independent degrees of freedom in two-dimensional materials* Sake Wang, F. R. Pratama, M. Shoufie Ukhtary, Riichiro Saito
3-9

3-10

Optical Properties of Monolayer Transition Metal Dichalcogenides on GaN Surface
Depending on their Polarity* Shinichiro Mouri, Yuma Komichi, Keisuke Shinokita, Kazunari Matsuda,
Tsutomu Araki
Anomalous polarized Raman spectra of TaP* Riichiro Saito, Pang Xiaoqi, Wang Tong, Nguyen Hungxxxiii

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特別講演Special Lecture

1S–1 ～ 1S–2
2S–1 ～ 2S–2
3S–1 ～ 3S–4

1S-1
Emergent phenomena at van der Waals interfaces○Masaki Nakano1,2
1

QPEC and Department of Applied Physics, The University of Tokyo, Tokyo 113-8656, Japan
2
RIKEN Center for Emergent Matter Science (CEMS), Wako 351-0198, Japan

Since the discovery of graphene, a family of layered materials with nanometer-scale
thickness called ‘2D materials’ and their integrated superstructures named ‘van der Waals(vdW) heterostructures’ have become an invaluable material platform for condensed-matter
research, providing intriguing properties and functionalities that are missing in their 3D bulk
counterparts. There, the most-frequently-used sample fabrication method has been ‘top-down’mechanical exfoliation combined with the pick-up and transfer methods, while ‘bottom-up’
molecular-beam epitaxy (MBE) should provide a complementary and unique approach in 2D
materials research. Successful examples are the application of MBE-grown monolayer films
to spectroscopic studies like ARPES and STM/STS measurements that require large-areamonolayer films, unveiling fundamental aspects of a variety of 2D materials emerging at themonolayer limit. From materials science viewpoint, however, one of the biggest advantages ofthe MBE-based approach apart from large-area synthesis should be that we can design andcreate novel material systems that could not be achieved by simple exfoliation based on bulk
crystals, although such attempts are almost missing in this rising research field.
We have recently established a versatile route to layer-by-layer epitaxial growth of a wide
variety of 2D materials on insulating substrates by MBE [1], opening a door for exploration of
emergent transport phenomena arising with reducing thickness [2-6] even based on
hardly-cleavable [2, 3] and/or thermodynamically-metastable [5, 6] compounds as well as at
the interface between dissimilar materials [7, 8]. In this presentation, we will introduce ourrecent achievements in particular on the emergent transport phenomena at the vdW interfaces.
The first topic is for the vdW heterostructures composed of insulating 2D materials [7], where
we found emergent electrical conduction despite that the individual materials are highly
insulating, which could be simply understood by taking into account the band alignment at theinterface and the relevant interface charge transfer. The second topic is for the vdW
heterostructures made of metallic 2D material and itinerant 2D ferromagnet [8], where wefound significant modulation of the magnetic properties including the magnetic anisotropy aswell as the transition temperature, which could be naturally understood by considering a
new-type of magnetic proximity effect mediated by Zeeman-type spin-orbit interaction.
[1] M. Nakano et al., Nano Lett. 17, 5595 (2017).
[2] Y. Wang et al., Appl. Phys. Lett. 113, 073101 (2018).
[3] M. Nakano et al., Nano Lett. 19, 8806 (2019).
[4] H. Matsuoka et al., submitted.
[5] Y. Tanaka et al., submitted.
[6] S. Yoshida et al., submitted.
[7] Y. Kashiwabara et al., Adv. Funct. Mater. 29, 1900354 (2019).
[8] H. Matsuoka et al., submitted.
Corresponding Author: M. Nakano
Tel: +81-3-5841-6871, Fax: +81-3-5841-6822, E-mail: nakano@ap.t.u-tokyo.ac.jp

-1-

1S-2
High resolution electron micrographs of serial brain tissue sections on
conductive carbon nanotube coated PET tape and neural microcircuit analysis○Yoshiyuki Kubota1,2
1Division of Cerebral Circuitry, National Institute for Physiological Sciences, Okazaki444-8787, Japan2
Department of Physiological Sciences, SOKENDAI, Okazaki 444-8787, JapanThe electron microscopy (EM)-based reconstruction of neuronal circuits from serial
ultrathin sections has attracted considerable recent attention, despite the emergence of superresolution microscopy, because EM is a reliable method for the diverse-scale analysis ofdense nanoscale details in biological structures. Here, we focus on the automatedtape-collecting ultramicrotome (ATUM) method which allows the collection of many serial
ultrathin sections of consistent quality quickly and automatically by producing ultrathin
sections on a tape that can be repeatedly imaged using SEM. Currently, the most commonlyused tape for ATUM is carbon coated (cc)-Kapton tape (polyimide film, DuPont, Wilmington,
USA), but it has deficiencies due to a relatively high sheet resistance (19-6530 Mohm/sq),
non-uniform carbon coating that causes mottled surface resistance, and scratching. Moreover,there is no assurance of a regular supply of high-quality cc-Kapton tape due to inconsistentindustrial production procedures. Therefore, an improved alternative tape would have avaluable role the field of ATUM-based EM. In this study, we address these issues byintroducing an improved tape and tissue staining protocol. We screened candidates and foundthat plasma-hydrophilized-carbon nanotube (CNT) tape is optimal due to its extremely highsurface conductivity (240-500 ohm/sq) and low endogenous signal, and it can provide highquality images of tissue sections with SEM. The ATUM-SEM method impressively alters
current research strategy using an electron microscope on functional architecture of the brain
microcircuit.
[1] Kubota Y et al., Front. Neural Circuits,fncir.2018.00098 (2018)[2]窪田芳之, 電子顕微鏡を使った革新的脳組織解析法―コネクトーム研究；実験医学増刊「脳神経回路と高次脳機能 スクラップ＆ビル
ドによる心の発達と脳疾患の謎を解く」（榎本和生，岡部繁男編集）羊土社、東京、p158-164,
ISBN 978-4-7581-0372-5 (2018)[3] Kubota Y et al., Nature Communications, 9,437 (2018)

Corresponding Author: Y. Kubota
Tel: +81-564-59-5282, Fax: +81-564-59-5284,
E-mail: yoshiy@nips.ac.jp

Figure 1-2-

Pipeline of the ATUM-SEM method

2S-1High power factor, completely organic thermoelectric nanocomposites
enabled by carbon nanoparticles○Jaime C. Grunlan 1,2,3
Department of Mechanical Engineering, Texas A&M University, USA
Department of Materials Science and Engineering, Texas A&M University, USA
1

2

3

Department of Chemistry, Texas A&M University, USA

In an effort to create a paintable/printable thermoelectric material, comprised exclusivelyof organic components, polyaniline (PANi), graphene, and double-walled carbon nanotubes(DWNT) were alternately deposited from aqueous solutions using the layer-by-layer assembly
technique. Graphene and DWNT are stabilized with an intrinsically conductive polymer,
poly(3,4-ethylenedioxythiophene): poly(styrene sulfonate) (PEDOT:PSS). A 1 µm thick film,
composed of 80 PANi/graphene-PEDOT:PSS/PANi/DWNT-PEDOT:PSS quadlayers (QL)
exhibits electrical conductivity () of 1.88 x 105
S/m and a Seebeck coefficient (S) of 120 µV/K,
producing a thermoelectric power factor (S2∙σ) of
2710 µW/(m∙K2) [1]. This is the highest value everreported for a completely organic material
measured at room temperature. Furthermore, thisperformance matches or exceeds that ofcommercial bismuth telluride. These outstanding
properties are attributed to the highly orderedstructure in the multilayer assembly. The
thermoelectric power output increased with thenumber of cycles deposited, yielding 8.5 nW at 80
QL for ΔT = 5.6 K. A simple thermoelectric
generator was prepared with selectively-patterned,
fabric-based system. The electric voltage generated
by each TE device increased in a linear Fig.1 (a) and (b) are images of the patterned
relationship with both ΔT and the number of TE and fabric-based 80 QL thermoelectric
generator modules connected with silver ink
legs, producing ~ 5 mV with just five legs and a and wires. (c) and (d) are TE voltage
ΔT of 9.7 K, as shown in Figure 1. By stabilizing, generated by the patterned PET film andnanotubes and graphene with nitrogen-rich fabric-based devices as a function of ΔT [1].
molecules, n-type multilayer thin films withrelatively high power factor have also been produced [2]. This unique TE coating system iswater-based and uses only organic components. For the first time, there is a real opportunity
to harness waste heat from unconventional sources, such as body heat to power devices in anenvironmentally-benign way.
[1] J. Grunlan et al. Adv. Energy Mater. 6, 1502168 (2016).
[2] J. Grunlan et al. Nano Energy 28, 426 (2016).
Corresponding Author: J. Grunlan
Tel: +1-979-845-3027, Fax: +1-979-845-3081,
E-mail: jgrunlan@tamu.edu

-3-

2S-2
Active site of nitrogen-doped carbon catalysts for fuel cell○Junji Nakamura1
1

Faculty of Pure and Applied Sciences, Tsukuba Research Center for Energy Materials
Science (TREMS), University of Tsukuba. 1-1-1 Tennodai, Tsukbua 305-8573, Ibaraki, Japan
Nitrogen-doped graphitic carbons as
non-Pt catalysts for oxygen reduction
reaction (ORR) have been paid muchattention
inrecentyears
becausecommercialization of fuel cells requires lessexpensive and abundant catalytic materials.
Identification of the active site ofnitrogen-doped carbon materials for ORR isthus urgently required, but still under debate.
Currently, the debate focuses on whether theactive site is created by pyridinic N (Nbonded to two carbon atoms) or graphitic N(N bonded to three carbon atoms, also called
substituted N or quaternary N). To determine
the active site conclusively, we preparedmodel catalysts of highly oriented pyrolytic
graphite (HOPG) with pyridinic N(pyri-HOPG) or graphitic N (grap-HOPG).
The active sites and adsorption properties Figure.1Structural and elemental characterization ofwere examined by ORR and post-ORR four types of N-HOPG model catalysts and their ORR(A) Optical image of patterned
X-ray photoelectron spectroscopy (XPS). We performance.
edge-N+-HOPG. (B) The AFM image obtained from thehave thus determined the active nitrogen region indicated by the yellow rectangle in (A). (C) 3D
species in carbon [1,2]. The graphitic-N representation of (B). (D) Line profile of the AFM
dopingwas
performedbymild image obtained along the blue line in (B). (E) N 1s XPS
bombardment with a nitrogen ion beam. To spectra of model catalysts. (F) ORR results for model
prepare the pyri-HOPG samples, edge catalysts corresponding to (E). Nitrogen contents of themodel catalysts are shown as inset in (F).
patterning was first performed bybombarding the sample with an Ar+ ion beam through a slit-patterned Ni mask as shown in
Fig.1 A-D. The edged HOPG samples were then exposed to NH3 at 973 K. The catalytic
performances of the model catalysts were measured by cyclic voltammetry (CV) in acidic
electrolyte (0.1 M H2SO4). It was found that the pyri- HOPG model catalyst shows highactivity at high voltages, compared to the very low ORR activities of the N-free model
catalysts (Fig.1 E, F). Since the pyri-HOPG sample is nearly free of graphitic N, the ORR
results indicate that it is pyridinic N rather than the graphitic N that reduces the ORR
overpotential and creates the active site. It is thus concluded that the ORR active sites innitrogen-doped carbon materials are created by pyridinic N.
[1] D. Guo, R. Shibuya, C. Akiba, S. Saji, T. Kondo, J. Nakamura, Science, 351, 361 (2016).
[2] S. K. Singh, K. Takeyasu, J. Nakamura, Advanced Materials, 1804297 (2018).

-4-

3S-1
Gating IR in Textiles
YuHuang Wang 1
1

Department of Chemistry and Biochemistry, University of Maryland, 8051 Regents Drive,
College Park, MD 20742, United States

Our human body absorbs and loses heat largely through infrared radiation that peaks ataround 10 µm. However, despite thousands of years’ development, none of our clothing
systems are capable of controlling this major heat exchange channel. The infrared propertiesof both clothing and our own skin are fixed at a nearly constant level, regardless of whether
one feels hot or cold. In contrast, many species in nature have evolved elegant strategies tomanipulate light for the purpose of cooling and surviving harsh environments. For instance,
Saharan silver ants feature triangular shaped hairs that can reflect near-infrared rays according
to the position of the sun to keep themselves cool, while the geckos of Madagascar havephotonic skins with changeable colors that can blend in the environment to hide frompredators. In this talk, I will discuss a clothing textile that is capable of dynamically gating
infrared radiation through the fabric in response to personal thermal discomfort. We show thatby simply coating triacetate-cellulose fibers with a thin layer of carbon nanotubes we canmodulate the infrared radiation through the fabric by as much as 35% as a function of therelative humidity of skin. Both opportunities and challenges ahead will also be discussed iftime permits.
[1] Zhang, X.; Yu, S.J.; Xu, B.B.; Li, M.; Peng, Z. W.; Wang, Y.; Deng, S.L.; Wu, X.J.; Wu, Z.P.; Ouyang, M.;
Wang, Y. H. Science 363, 619-623 (2019).
[2] Xu, B.B.; Peng, Z.W.; Wu, Z.P.; Zhang, X.A.; Wang, Y. H. Reviews of Scientific Instruments 90, 113102(2019).
Corresponding Author: Y. H. Wang
Tel: +1-301-405-3368
E-mail: yhw@umd.edu

-5-

3S-2
Selective growth of single walled carbon nanotubes: thermodynamics versus kinetics
Christophe Bichara
Centre Interdisciplinaire de Nanoscience de Marseille ‐ CINaM
CNRS and Aix‐Marseille University, Marseille, France

In classical crystal growth, the interaction of the growing object with its support and the energies ofthe different facets determine the growth mode and the resulting crystalline structure. The synthesisof carbon nanotubes by chemical vapor deposition poses somewhat similar yet more complex issues.
The catalytic particle is both a support and a reactive interface with the growing tube, and many
properties are altered because of the nanometric size of the objects. With this in mind, we haveidentified different growth modes driven by the thermodynamic properties of the interface [1, 2] anddeveloped a modeling of the interface [3], emphasizing the importance of the configurational entropyof the nanotube edge to stabilize chiral tubes and to account for the temperature dependence of tubes’
helicity distributions.
We present here further developments of this very simple thermodynamic model, including moregeneral interface structures and the corresponding evaluation of the entropy. We also use Monte Carlosimulations to analyze the growth mechanisms and related growth rates, to address the process
kinetics in relation with the chiral selectivity of the synthesis.
References[1] Fiawoo, M.‐F. C. et al. Phys. Rev. Lett. 108, 195503 (2012).
[2] He, M. et al. Nanoscale 10, 6744, (2018)[3] Magnin, Y. et al., Science 362, 212–215 (2018)

-6-

3S-3
In situ Study of Catalysts for Single-Walled Carbon Nanotube
GrowthFeng Yang and Yan Li
College of Chemistry and Molecular Engineering, Peking University, Beijing 100871,
China
Metallic Co and intermetallic compound Co7W6 are both catalysts for the growth of
single-walled carbon nanotubes (SWCNTs) but have shown great difference in thechirality selectivity. We studied the composition and structure of Co and Co7W6
nanocrystals in methane, carbon monoxide, and hydrogen at the temperature of 700–
1100 oC by using environmental aberration-corrected transmission electron microscopy
in combination with in situ synchrotron X-ray absorption spectroscopy. we directly
present the structural and composition evolution of cobalt catalysts during thenucleation and growth of SWCNTs under carbon feeding. In the case of Co
nanoparticles, the co-existence of cobalt and cobalt carbide was generally observed
among the catalysts which are active in nucleating tubes. It was found that the tubes
grown from solid state Co nanoparticles always present smaller diameter than the
catalysts and no structure-correlation between catalyst and nanotube was found.
However, the structure and chemical composition of the Co7W6 nanocrystals werestable under the atmosphere of methane, carbon monoxide, and hydrogen at hightemperature. The SWCNTs grown from Co7W6 nanocrystals also show smaller
diameter than the catalysts. But the distribution of the tube diameters is discrete. The
above observations reveal the difference in growth mechanism of the two types ofcatalysts.

Corresponding Author: Yan. Li
Tel & Fax: +86-10-6275-6773
E-mail: yanli@pku.edu.cn

-7-

3S-4
Nanoscale optical and vibrational spectroscopy of low-dimensional
materials in electron microscope○Ryosuke Senga1, Kazu Suenaga1, Thomas Pichler2
1

Nanomaterial research institute, AIST, Tsukuba 305-8565, Japan
2
Faculty of Physics, University of Vienna, Vienna, Austria

Excitations of quasiparticles govern physical properties of low-dimensional materials.
Especially their behaviors at non-perfect structures like boundaries, edges, defects or irregular
stacking sequence are undoubtedly important to understand the performance of nanodevices
consisting of nanomaterials. However, such local information has been usually averaged inconventional inelastic scattering techniques using x-ray, neutron and light sources because of
their diffraction limit. Here we demonstrate the nanoscale optical and vibrational
spectroscopy of 1D/2D materials by using a monochromatic electron source mounted in ascanning transmission electron microscope. Its energy resolution, better than 30 meV, allows
to access the quasiparticle excitations (i.e. phonon, exciton and plasmon) of low-dimensional
materials by electron energy-loss spectroscopy (EELS). The spatial and momentum
resolutions balance each other and can be finely tuned with magnetic/electrostatic lenses. For
instance, an atomically thin probe can be formed with an integration of large momentum
space. This allows us to extract local information from single defects. Indeed, we havesuccessfully measured the optical gap transitions from a defect of an individual
semiconducting carbon nanotube [1,2]. In contrast, an electron probe with a higher
momentum resolution can provide a full phonon dispersion of 2D materials (Fig. 1) such as
hexagonal
boron
nitride or graphene ata few tens nanometerscale [3]. Thus, thepropagation of eachphonon mode at
defects such as edges
in graphene has been
unambiguously
visualized. This local
spectroscopy with alarge flexibility will
open up a wide Fig. 1 Experimental setup for the momentum-resolved EELS and examples ofpossibility to unravel momentum-resolved EEL spectra taken at q=2.25 and 4.00 Å-1 along the GMGM
the defect physics of direction. The spectrometer entrance aperture is placed at a given position in thequantum matters.
diffraction plane including the first, second, or third Brillouin zones.
[1] R. Senga, T. Pichler and K. Suenaga Nano Letters 16, 3661 (2016).
[2] R. Senga et al., Nano Letters 18, 3920 (2018).
[3] R. Senga et al., Nature 573, 247 (2019)
Corresponding Author: R. Senga
Tel: +81-29-862-6518
E-mail: ryosuke-senga@aist.go.jp

-8-

招待講演
Invited Lecture

1I–1

1I-1
FC-CVD synthesis of CNTs from methane for transparent conductor
applications.
Qiang Zhang, Datta Sukanta, Hua Jiang, Esko I. Kauppinen
Department of Applied Physics, Aalto University School of Science, PO Box 15100,
FI-00076 Aalto, Espoo, FINLAND
Due to scalability, low-cost and good control of carbon nanotube (CNT) synthesis, floating
catalyst chemical vapor deposition (FC-CVD) keep attracting intense attention in bothacademic and industrial fields [1,2]. Especially, the CNT aerosol from FC-CVD can be directly
deposited into transparent conducting films (TCFs) which are critical components of many
optoelectronic devices that pervade modern technology [1]. Currently, one of the ideal modelsof high-performance CNT TCFs is the net-work containing long, straight, individual,
high-quality single-wall CNTs (SWCNTs) [3]. Many efforts in FC-CVD have been devoted toincreasing the conductivity of CNT TCFs based on this model. However, intrinsic nanotube
collisions in the aerosol process of FC-CVD lead to a tread-off between yield and performance[3], because bundling increases when increasing the yield i.e. production rate, with the bundlingincreasing sheet resistance at the given film transmittance. Here, we report TCFs oflarge-diameter CNTs from methane-based FC-CVD overcoming the performance–yield
tradeoff. Based on the Fe-C-S system, the double-wall CNTs (DWCNTs) with a mean diameterof 4.15 nm and a mean bundle length of 20 um have been produced into TCFs via FC-CVD.
After gold chloride solution doping, the TCFs have an excellent performance of 42 ohm/sq
sheet resistance at 90% transmittance. Unexpectedly, these high-performance DWCNTs films
have an ultra-high yield i.e. production rate, being two orders of magnitude higher than that of
SWCNT based TCFs with similar performance. Especially, these high-yield DWCNTs films
contain ‘small’ bundles with around 50% of CNTs being individual, which is completely
different from other FC-CVD results for SWCNTs produced at much lower yield. Moreover,the large-diameter DWCNTs will flatten at the junctions, which can provide a larger contact
area between the tubes and reduce the contact resistance. These unique features oflarge-diameter CNTs in ‘small’ bundles are the key to obtain high-performance CNT TCFs
with high yield. These results imply a new model with optimization windows forhigh-performance CNT TCFs with high yields and accordingly at reduced cost, and may
accelerate the practical application of CNTs TCFs.
[1] Zhang, Qiang, et al. Topics in Current Chemistry, 99-128 (2019).
[2] Liao, Yongping, et al. Journal of the American Chemical Society 140.31 (2018).
[3] Mustonen, Kimmo, et al. Applied Physics Letters 107.14 (2015).
Corresponding Author: Esko I. Kauppinen
Tel: +358 40 509 8064 Fax: +358 9 2451 3517
E-mail: esko.kauppinen@aalto.fi

-9-

2I-2

- 10 -

記念セッション
Commemorative Session

2C–1 ～ 2C–6

2C-1The beginning of nano-carbon era― Prediction and discovery of C60―
○Yohji Achiba
Department of Chemistry, Tokyo Metropolitan University, Tokyo 192-0397, Japan
Nano carbon materials so called “fullerenes” are closed-cage molecules containing only
pentagonal and hexagonal rings, of which the celebrated icosahedral C60 molecule is thearchetype. Although hollow-shell graphite molecules were mentioned in the scientificdiversions column in 1966, the first article of the theoretical speculation on the possibility of a
sixty-carbon framework based on the truncated icosahedron was published fifty years ago in1970 by Osawa1) in the study of “superaromaticity”.
Like so many important scientific discoveries, experimental evidence of the predicted C60
structure suddenly appeared while alert individuals were looking for something else. In 1985,
Kroto, Heath, O’Brien, Curl and Smalley were studying the formation of long-chain carbon
molecules in circumstances analogous to interstellar space and stellar atmospheres. Theyobserved that under certain conditions, clusters consisting of sixty carbon atoms were
produced in unusual abundance. The truncated icosahedron C60 cage structure was proposed
and then named “buckminsterfullerene”, because geodesic dome concepts had played an
important part in the arriving at their solution.
An explosive of fullerene research occurred with the invention of techniques for the
production and isolation of bulk quantities of fullerenes by Kraetschmer, Lamb, Fostiropoulos
and Huffman in 1990. Since then, due to the relative simplicity of the sample preparation,
many research groups have been able to bring tools and insights of their specialty to the studyof fullerenes. The present talk is an attempt to bring a brief history of the discovery of C60
molecule by which so called nano-carbon era has certainly begun.

[1] E. Osawa, Kagaku (Kyoto) 25, 245 (1970)[2] H. W. Kroto, J. R. Heath, S. C. O’Brien, R.F. Curl, and R. E. Smalley, Nature, 318, 162 (1985).
[3] W. Kraetschmer, LO. D. Lamb, K. Fostiropoulos, and D. R. Huffman, Nature, 347, 354 (1990).
Corresponding Author: Y. Achiba
Tel: +81-42-677-2534,
E-mail: achiba-yohji@tmu.ac.jp- 11 -

2C-2
C60 as a carbon cluster○Susumu Saito1-3
Department of Physics, Tokyo Institute of Technology,
2-12-1 Oh-okayama, Meguro-ku, Tokyo 152-8551, Japan
2
Advanced Research Center for Nanoscience and Quantum Physics,
Tokyo Institute of Technology, 2-12-1 Oh-okayama, Meguro-ku, Tokyo 152-8551, Japan
3
Materials Research Center for Element Strategy, Tokyo Institute of Technology,
4259 Nagatsuta-cho, Midori-ku, Yokohama, Kanagawa 226-8503, Japan1

In 1980s, the field of “clusters”, the systems of finite number of atoms, emerged as one of
new exciting research fields due to the development of experimental techniques to deal withclusters and to the advancement of first-principles electronic-structure theory, and Japanese
researchers have played many important roles to further develop the field which is now callednanoscience and nanotechnology. I will review the history of cluster research field from theviewpoint of physics, and discuss the importance of the prediction of C60 by Professor Eiji
Osawa in 1970 in this field.
Corresponding Author: S. Saito
E-mail: saito@stat.phys.titech.ac.jp- 12 -

2C-3
TEM Observations of Carbon: Amorphous, Fullerenes andCarbon nanotubes
Sumio Iijima
Meijo University, Graduate School of Science and Technology
University Professor of Nagoya University & NEC Senior Research Fellow
In early years of development of amorphous silicon for solar battery (1970s), there was a
big dispute concerning what is the atomic structure of amorphous silicon.
Knowing this issue, I started to examine amorphous carbon films that have been familiar
among electron microscopists.
During those studies I came across onion-like spheres of graphite (1980).
The TEM pictures of the onions were appreciated by Kroto & Smalley, discoverers offullerene, because the picture supports their postulated C60 model (1987).
It was 8 years before they received Nobel prize.
In this way I was acquainted with them, and they persuaded me to work on fullerene, andsoon later, fortunately I discovered carbon nanotubes (1991).
By the way, google citation of the Nature paper reached more than 50,000.

Corresponding Author: S. Iijima
Phone/Fax: +81-(0)52-834-4001,
E-mail: iijimas@meijo-u.ac.jp- 13 -

2C-4
The 50 years of a soccer-ball molecule C60†
Eiji Osawa
Nanocarbon Research Institute Co., Ltd., Ueda, Nagano 386-8567, Japan
Interviewed by
Masaki Ozawa1 and Tomonari Wakabayashi2
1

Department of Applied Chemistry, Meijo University, Nagoya 468-8502, Japan
Department of Chemistry, Kindai University, Higashi-Osaka 577-8502, Japan2

In 1970, Eiji Osawa issued a prophetic idea for aromatic stability of a soccer-ball molecule,namely C60, from a saucer-shaped hydrocarbon molecule, corannulene, as a building block [1].
Upon 50-years anniversary of his earliest record of the truncated icosahedral molecule (Fig. 1),
we trace back the story from the original idea to the series of epoch-making events succeeding
afterward: the discovery of the ultra-stable gas-phase carbon cluster, Buckminsterfullerene, in1985 [2] and explosion of experimental as well as theoretical researches triggered by the
preparation of macroscopic amounts of C60 as a new form of solid carbon in 1990 [3], eventuallyleading to the detection of C60 in space [4,5]. The story is more than most dramatic dramas, inwhich a vast number of researchers have been involved successfully or unsuccessfully.
Since 1991, The C60 Research Society, currently The Fullerenes,
Nanotubes and Graphene (FNTG) Research Society, has been themost active interdisciplinary forum for exchange and collaborationof researchers from a wide variety of fields, i.e., physics, chemistry,mathematics, astrophysics, biology, electrical and mechanicalengineering, and materials science in particular. Professor Eiji Osawa
had long been servicing as The First President of The Society during
the period of 1991-2003. He is now Head of Nanocarbon ResearchInstitute and pursuing a long-standing issue on the formation
Fig. 1 A soccer-ballmechanism of C60 in natural environments including detonation
molecule in 1970 [1].
diamonds and nanodiamonds.
[1] E. Osawa, Kagaku 25, 854 (1970); Z. Yoshida & E. Osawa, Aromaticity, Kagaku Dojin, p.p. 174-178 (1971).
[2] H. W. Kroto, J. R. Heath, S. C. O’Brien, R. F. Curl, and R. E. Smalley, Nature 318, 162 (1985).
[3] W. Krätschmer, L. D. Lamb, K. Fostiropoulos, and D. R. Huffman, Nature 347, 354 (1990).
[4] J. Cami, J. Bernard-Salas, E. Peeters, and S. E. Maleck, Science 329, 1180 (2010).
[5] E. K. Campbell, M. Holz, D. Gerlich, and J. P. Maier, Nature 523, 322 (2015).
Topic in The Special Session, FNTG58, dedicated to Professor Eiji Osawa for his prediction of icosahedral C60.
Executive Committee Members: Tomonari Wakabayashi, Toshiki Sugai, Taishi Takenobu, and Susumu Okada.
Advisory Panel: Susumu Saito. Reprint Production: Yutaka Matsuo is acknowledged for his efforts to realize kindoffer by Kagaku Dojin of 300 copies with English translation of the original article in Japanese in 1970 [1].

†- 14 -

2C-5
Unveiling the origin of cosmic fullerenes through investigations into physicalproperties of fullerene-containing planetary nebulae◦M. Otsuka1 , F. Kemper2 , J. Cami3,4 , E. Peeters3,4 , and Fullerene PN consortium
1 Okayama Observatory, Kyoto University, 719-0232 Okayama, Japan
2 European Southern Observatory, Karl-Schwarzschild-Str. 2, 85748 Garching b., München,
Germany
3 The University of Western Ontario, London, ON N6A 3K7, Canada
4 SETI Institute, 189 Bernardo Ave, Suite 100, Mountain View, CA 94043, USA
Since the prediction of the existence in 1970 [1] and their laboratory discoveries in 1985[2], fullerenes have drawn considerable interest from astrochemists looking for them in circumstellar and interstellar conditions; because fullerenes are extremely stable and easily formed inlaboratories on Earth, and therefore it had been thought that they should abundantly exist evenin interstellar space. However, the first confirmed detection of cosmic fullerene C60 and C70
emission at mid-infrared wavelengths was only recently reported in the carbon-rich (i.e., thenumber density ratio of C/O > 1) planetary nebula (PN) Tc1 [3] with mid-infrared space telescope Spitzer [4]. PNe are in the last evolutionary phase of Sun-like stars of the initial 1 − 8solar mass, and more than 3000 PNe have been found in the Milky Way galaxy, so far. After the detection report by [3], spectroscopic observations by Spitzer detected fullerenes in avariety of space environments. At the moment, PNe represent the largest fraction of fullerene
detection; 24 fullerene-containing PNe have been identified in the Milky Way galaxy and theMagellanic Clouds [5-10, references therein]. Emission from planner graphene sheet C24 is potentially detected in some PNe [7]. Thus, the case of the detection has been increased, however,it remains unclear why these objects exhibit fullerene features and how fullerenes were formedin such evolved star environments. To answer these questions is directly related to understandthe formation and evolution of large organic molecules in the solar system. Therefore, wehave investigated physical properties of fullerene-containing objects, in particular, PNe basedon multiwavelength data [8-10]. In this talk, we introduce our recent results and also discuss
potential collaboration between astrophysicists and chemists towards understanding the originof cosmic fullerenes.
[1] E. Osawa, Kagaku, 25, 854 (1970).
[2] H. W. Kroto et al. Nature, 318, 162 (1985).
[3] J. Cami et al. Science, 329, 1180 (2010).
[4] http://www.spitzer.caltech.edu[5] J. Bernard-Salas et al. ApJ, 757, 41 (2012).
[6] D. A. Garcı́a-Hernández et al. ApJ, 760, 107 (2012).
[7] D. A. Garcı́a-Hernández et al. ApJ, 737, 30 (2011).
[8] M. Otsuka, MNRAS, 482, 4354 (2019).
[9] M. Otsuka et al. MNRAS, 462, 12 (2016).
[10] M. Otsuka et al. MNRAS, 437, 2577 (2014).
Corresponding Author: M. Otsuka
Tel: +81-865-47-0138, Fax: +81-865-47-0139,
E-mail: otsuka@kusastro.kyoto-u.ac.jp- 15 -

2C-6
Curved nanocarbon molecules from concise and versatile synthesis
簡便・汎用合成が生み出す湾曲ナノカーボン分子
Hiroyuki Isobe

Department of Chemistry, The University of Tokyo, Hongo, Tokyo 113-0033, JapanJST ERATO Isobe Degenerate π-Integration Project, Hongo, Tokyo 113-0033, Japan"A sphere made of sp2-carbon atoms." This anomalous structure of [60]fullerene wasa spark to ignited a new science of curved π-systems. A series of unique curved structures
emerged from the planar trigonal structure of sp2-carbon atoms, which revealed anomalous
properties of the curved systems. Synthetically, the synthesis of curved π-molecules has been,and still is, a challenge for chemists. Introduction of a conceptually new "planar trigonal"
structure with 1,3,5-trisubstituted benzene (named "phenine") opens up a new stream of
curved π-design, and our explorations of the first series of "geodesic phenine molecules" will
be presented at the symposium.

Fig. Geodesic phenine frameworks; the first series.
[1] Ikemoto, K.; Kobayashi, R.; Sato, S.; Isobe, H. Angew. Chem. Int. Ed. 2017, 56 (23), 6511-6514. Ikemoto,K.; Kobayashi, R.; Sato, S.; Isobe, H. Org. Lett. 2017, 19 (9), 2362-2365.
[2] Ikemoto, K.; Lin, J.; Kobayashi, R.; Sato, S.; Isobe, H. Angew. Chem. Int. Ed. 2018, 57 (28), 8555-8559.
[3] Finite phenine nanotubes with periodic vacancy defects. Sun, Z.; Ikemoto, K.; Fukunaga, T.M.; Koretsune,
T.; Arita, R.; Sato, S.; Isobe, H. Science 2019, 363 (6423), 151-155. Sun, Z.; Mio, T.; Ikemoto, K.; Sato, S.;
Isobe, H. J. Org. Chem. 2019, 84 (6), 3500-3507.
Tel: +81-(0)3-5481-4777, Fax: +81-(0)3-5841-4162; Web: https://www.chem.s.u-tokyo.ac.jp/users/physorg/
E-mail: isobe@chem.s.u-tokyo.ac.jp- 16 -

一般講演
General Lecture

1 – 1 ～ 1 – 13
2–1 ～ 2–5
3 – 1 ～ 3 – 10

1-1
One-pot Separation of Semiconducting Single-walled Carbon Nanotubes Based on
Supramolecular Chemistry
Naotoshi Nakashima
International Institute for Carbon-Neutral Energy Research, Kyushu University, Fukuoka,
Japan
The separation/purification of semiconducting single-walled carbon nanotubes (sem-SWNTs)
with high quality is one of the most important issues in the science and technology of carbon
nanotubes. In the meeting, I summarize our developed supramolecular chemistry-based onepot separation of sem-SWMTs. The methods contain:i)use of fluorene copolymers with a (n,m)chirality recognition moiety[1-7] andenantiomer recognition moiety [8 ]ii)use of a supramolecular coordination polymer [9] : adsorbent removable systemiii)
use of a hydrogen bonding supramolecular system [10] : adsorbent removable systemiv)
use of assembled flavin molecules with thioalkyl substituents at 7- and 8 positions [1114]: adsorbent removable system
References[1] N. Nakashima et al., Chem. Lett., 40, 239-241 (2011).
[2] N. Nakashima et al., Chem. Lett. 40, 470-472 (2011).
[3] N. Nakashima et al., Chem. Eur. J. 17, 13438-13444 (2011).
[4] N. Nakashima et al., J. Am. Chem. Soc., 133, 14771–14777(2011).
[5] N. Nakashima et al., Nanoscale, 2014, 6, 5879–588.
[6] N. Nakashima et al., Chem. Eur. J., 2015, 21, 3359-3366.
[7] N. Nakashima et al., Polymer Chem. 2015, 6, 5103-5109.
[8] N. Nakashima et al., J. Am. Chem. Soc. 2012, 134, 12700-12707.
[9] N. Nakashima et al., Nature Communications, 2014, 5, art no. 5041.
[10] N. Nakashima et al., Scientific Reports, 2015, 5, art. no.18066.
[11] N. Nakashima et al., Chem. Lett. 2015, 44, 566-567.
[12] N. Nakashima et al., Bull. Chem. Soc. Jpn. 2018, 91, 1646-1651.
[13] N. Nakashima et al., Bull. Chem. Soc. Jpn. 2019, 92, 1679-1683.
[14] N. Nakashima et al., submitted
Corresponding Author: N. Nakashima
Tel: +81-92-802-6745
E-mail: nakashima.naotoshi.614@m.kyushu-u.ac.jp- 17 -

1-2
Fast synthesis of vertically aligned CNTs arrayexceeding one-centimeter height○Shunsuke Sakurai, Takashi Tsuji, Maho Yamada, Kenji Hata, Don N. Futaba
CNT-Application Research Center, National Institute of Advanced Industrial Science andTechnology (AIST), Tsukuba, Ibaraki 305-8565, Japan
Vertically aligned arrays of long carbon nanotube (CNT) have attracted much attention due
to its potential for the application such as electrodes and actuators. Although many groups
demonstrated the synthesis of millimeter-long CNT arrays [1], centimeter-long CNT array has
been rarely reported. Cho et al. has reported record-long (21.7 mm) MWNT array by using
Fe-Gd catalyst, instead of commonly used Fe catalyst, with maintaining catalyst lifetime up to
790 minutes [2]. In contrast, an advance of catalyst support material from a commonly used
Al2O3 layer was rarely studied yet.
In this paper, a wide variety of double-layered catalyst support system, composed of a verythin (c.a. 1 nm) top layer (Al2O3 or MgO) deposited on a thick bottom layer (various metaloxides such as Al2O3, MgO, SiO2, HfO2, or ZrO2) has been demonstrated to enhance catalyst
lifetime and the resulting CNT array height. Especially, a specific combination of top/bottom
layer, c.a. 2-3 nm as-sputtered Al2O3 top layer with >100 nm SiO2 (thermally-grown from Si
wafer) bottom layer, has been found to have an unexpected effect to enhance the initial
growth rate of CNT array. As a result, a uniform CNT array exceeding 10 mm height was
obtained after only 60 minutes growth (Fig.1).
Our detailed study shows the importance of
annealing procedure in prior to the supply ofcarbon feedstock to catalyst substrate.
[1] K. Hata, D. N. Futaba, K. Mizuno, T. Namai, M.
Yumura, and S. Iijima, Science 306, 1362 (2004).
[2] W. Cho, M. Schulz, and V. Shanov, Carbon 72,
264 (2014).
Corresponding Author: S. Sakurai
Tel: +29-861-6205, Fax: +81-29-861-4851,
E-mail: shunsuke-sakurai@aist.go.jp- 18 -

Fig.1 Photograph of CNT array exceeding 1 cm
height.

1-3
Luminescence of CNTs by luciferin/luciferase reaction from firefly○Takeshi Tanaka, Mahoko Higuchi, Atsunori Hiratsuka, Hiromichi Kataura
Nanomaterials Research Institute, National Institute of Advanced Industrial Science andTechnology (AIST), Tsukuba 305-8565, Japan

Luminescence (a.u.)

Figure 2[1] Y. Yomogida et al. Nat. Commun. 7, 12056 (2016).
Corresponding Author: T. Tanaka
Tel: +81-29-861-2903, Fax: +81-29-861-2786,
E-mail: tanaka-t@aist.go.jp- 19 -

Luminescence

Absorbance

Near infrared (NIR) light emission from carbon nanotubes (CNTs) draws great attention to
medical applications, such as bio-imaging, because NIR light shows high-transparency andlow-scattering in biological tissues [1]. Although photoluminescence is widely used for theapplications, there is a problem that visible excitation light cannot reach deep part of thetissues. In this study, we tried to utilize the luminescence reaction of firefly luciferase toexcite CNTs and successfully obtained NIR
18000
luminescence derived from CNTs. Because the NIR
luminescence of CNTs by luciferase does not need
6000
external excitation light, it could be powerful tool forbio-imaging at deep tissues.
0.5
4000
The luminescence reaction catalyzed by firefly
luciferase uses luciferin, ATP, and O2 as substrates
2000
and produces luminescence at ~562 nm (Fig. 1,00
broken line). CoMoCAT-CNT (SG65) containing
200
400
600
800
1000
1200
1400
Wavelength(nm)(6,5) CNTs as a major component was chosen to
prepare aqueous dispersion, because the excitation
Fig. 1 Luminescence spectrum by(S22) wavelength of (6,5) CNTs (~570 nm) matches
luciferin/luciferase reaction fromthe luminescence wavelength by luciferase reaction.
firefly (broken line) and absorption
spectrum of CoMoCAT-CNT aqueous
Although the difference of the signal with or without
dispersion (solid line).
CNTs was very small, we could detect theluminescence of CNT/luciferase system using IR
1camera. After optimization of the reaction condition,such as concentrations of substrates and luciferase, pH,
0.8
CNTs, etc., luminescence spectrum of the reaction
0.6
could be taken by a spectrophotometer (Fig. 2). The
0.4
peak wavelength of the luminescence was consistent
0.2
with that of photoluminescence of (6,5) CNTs (984nm), indicating the luminescence of CNT/luciferase
0
800
900
1000
1100
1200
1300
system is derived from (6,5) CNTs. Detailed results
Wavelength (nm)are given at the symposium.
Fig. 2 Luminescence spectrum ofThis work was partly supported by KAKENHI No.
(6,5) CNTs excited by luciferase
19H02539 and Suzuken Memorial Foundation.
reaction.

1-4
Selective Activation of Singlet/Triplet Reaction Paths Enabled by
Carbon-nanotube-mediated Energy Attenuation○Dongxin Liu1, Dominik Lungerich1, Satori Kowashi1, Takayuki Nakamuro1,
Kaoru Yamanouchi1, Koji Harano1, Eiichi Nakamura1
1

Department of Chemistry, The University of Tokyo, Tokyo 113-0033, Japan

In spite of its long history of application of an electron beam (e-beam) for a variety ofchemical applications, e-beam has scarcely considered as an energy source for a precise
control of molecular transformations. In this context, our group recently demonstrated [1] that
[2 + 2] cyclization of C60 molecules (denoted as C60 dimerization) in carbon nanotubes(CNTs) can be controlled by e-beam. In the report, we performed single-molecule kinetics
through video-imaging by transmission electron microscopy: we counted events of C60
dimerization one by one and provided rate constants based on observation of several tens of
the events. In this work, we investigated the effects of e-beam with variable energy and foundthat CNTs attenuate the energy of e-beam and enable selective activation of singlet/triplet
reaction paths of C60 dimerization.
Following the previous report [1], single-molecule kinetic study of C60 dimerization was
conducted at 393-493 K with e-beam of 60-120 keV. With an e-beam of 60 keV, C60
dimerization did not take place. However, the dimerization took place with an e-beam of 80,
100 and 120 keV. We observed two activation energies (Ea), 13 kJ/mol at 80 keV and 34
kJ/mol at 100 and 120 keV, that are ascribed to two different excited states. Since the [2 + 2]
dimerization is ground-state-forbidden, we assigned the path with the lower Ea at 80 keV totriplet (T1), and the one with the higher Ea at 100 and 120 keV to singlet (S1), following theorder of e-beam energy. Because the energy of such electrons is over ten thousand times
higher than that of the excited states of C60 molecule (1.6–2.0 eV), we suggest that the CNT
container attenuates the energy of e-beam by the factor of 10–5, and thus the energy given to
the molecules becomes small enough to enable spin-state-selective electronic excitations.
(a)

(b)

e– Beam Ground-state-forbidden[[2+2] Dimerizatione-beam[2 + 2] cyclization

Singlet path

100, 120 keV
e-beam80 keVe-beam

CNT
CNT*
CNT*
CNT

Triplet path

C60* (S1)

C60

+ C60

+ C60

C60* (T1)

+ C60

C120*

C120
C120*

Fig.1 Selective activation of singlet/triplet reaction paths. (a) TEM images and schematic
drawings of [2 + 2] cyclization of C60 molecules. (b) Processes of energy attenuation mediated bycarbon nanotubes (CNTs).
[1] S. Okada et al. J. Am. Chem. Soc. 139, 18281 (2017).
Corresponding Author: K. Harano and E. Nakamura
Tel: +81-3-5841-4369, Fax: +81-3-5841-4367,
E-mail: dongxin@chem.s.u-tokyo.ac.jp- 20 -

1-5
Polyaromatic Anthracene Nano-tweezer on Semiconducting Carbon
Nanotubes for Growth and Bridging of Perovskite Crystal Grains in
Perovskite Solar Cells○Hao-Sheng Lin 1, Shuhei Okawa,1 Il Jeon 1, Yutaka Matsuo 1, Shigeo Maruyama 1
1

Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan

Polyaromatic anthracene, which contains a bent polyaromatic group on one end and afunctional group on the other end, has been reported to clench SWNTs. While thepolyaromatic end induces strong π-π interaction with the SWNTs, the functional end caneasily be modified chemically. In our group, the modified polyaromatic anthracenes wereused as charge-transporting layers in optoelectronics, harnessing their bandgaps and highmobility arising from the conjugated sp2 bonds. Hence, we designed and synthesized
4,6-di(anthracen-9-yl)-1,3-phenylene bis(dimethylcarbamate) (DPB), which is essentiallypolyaromatic anthracene with two urea-analogues functional groups. Subsequently, we usedthem as new surfactants for s-SWNTs in the PSC application. DPB successfully attached tos-SWNTs and replaced DOC surfactants as confirmed by photoluminescence (PL) andUV-visible absorption spectroscopy (UV-Vis). DPB-attached s-SWNTs showed much higher
solubility in both DMF and dimethyl sulfoxide (DMSO) than the DOC-attached s-SWNTs.
Accordingly, higher concentration of s-SWNTs could be added to the perovskite precursor
solution. The DPB on SWNTs expectedly manifested a stronger interaction on Pb2+ than DOC
owing to the strongly electron donating nature of the lone pair electrons on the carbamate
group enhanced by its configurational orientation facing outwards. DPB-attacheds-SWNT-added perovskite films exhibited excellent charge-selectivity and reduced charge
trap density. The suitable molecular energy levels and higher mobility of DPB compared with
DOC led to higher device performance. DPB-attached s-SWNTs-added PSCs exhibited a PCEof 20.7%, which is higher than those of DOC-attached s-SWNT-added PSCs (19.7%) andpristine PSCs (18.4%). All of the three photovoltaic parameters, namely, high short-circuitcurrent density (JSC), open-circuit voltage (VOC), and filling factor (FF) contributed to the highpower conversion efficiency (PCE) of the DPB-attached s-SWNTs-added PSCs. The high JSC
came from the large perovskite crystal size of over 500 nm. The high VOC came from strong
passivation effect of the DPB-attached s-SWNTs. The high FF came from the improved
carrier mobility and charge selectivity of DPBs on s-SWNTs.

Corresponding Author: S. Maruyama
Tel: +81-3-5841-6408
E-mail: maruyama@photon.t.u-tokyo.ac.jp- 21 -

1-6
Optimization of the Alignment Relay Technique for the Controlled
Orientation and Selection of Single-Walled Carbon Nanotubes○Monika Snowdon1, Derek Schipper 1, Dai-Ming Tang 2
1

Department of Chemistry, University of Waterloo, ON, N1G 2L9, Canada
2
National Institute for Materials Science, Tsukuba 305-0044, JapanThe semiconducting industry has grown immensely over the last 40 years, moving
towards smaller and faster devices that correspond with the predictions of Moore’s law.
However, current technology cannot be tailored to progressively smaller dimensions withoutcompromising functionality. Instead, advances in the manipulation of nanomaterials canresolve this challenge and provide information on the chemical-physical properties needed forhigher-performance electronics at significantly smaller dimensions. Within these lines, one
possibility is to replace silicon transistors with single-walled carbon nanotubes (SWNTs). [1]Nonetheless, there are a few problems that must be solved before SWNTs can be integrated
into devices. The main difficulty is separation of the diverse kinds of SWNTs, as only certain
tube conformations have the desirable semiconducting properties. [2] Additionally, SWNTs
favor a random conformation when deposited onto a surface, which renders them ineffective;
therefore, assembling them into tight alignment with one another is quite a complex
challenge.[3] In this work, we portray the alignment relay technique (ART) for thesimultaneous alignment and sorting of SWNTs toward transistor applications. The techniqueand methods for improving alignment will be discussed. and an example of the aligned
molecules interacting with the SWNTs is schematically represented in Figure 1.

Fig.1 Schematic example of the alignment relay technique (ART) on controlling the orientation of
single-walled carbon nanotubes (SWNTs).
[1] Baughman, R. H.; Zakhidov, A. A.; de Heer, W. A. Science. 297, 787-792 (2002).
[2] Cao, Q. et al. Science. 350, 68-72 (2015).
[3] Ieong, M.; Doris, B.; Kedzierski, J.; Rim, K.; Yang, M. Science. 306, 2057-2060 (2014).
Corresponding Author: D. Tang
Tel: +81-0-29-859-2000, Fax: +81-0-29-859-2029
E-mail: tang.daiming@nims.co.jp- 22 -

1-7
Fabrication of graphene nanoribbon homojunction for transport gap
control○Noritada Ogura1, Toshiro Kaneko1, and Toshiaki Kato1,2
1

Graduate School of Engineering, Tohoku University, Sendai 980-8579, Japan
2
JST-PRESTO

Graphene nanoribbon (GNR), strips of two-dimensional (2D) graphene into
one-dimensional (1D) structure, attracts intense attentions because of their novel electricalfeatures. Although GNR can be synthesized by various methods, the reliable site andalignment control of GNR with high on/off current ratio remains a challenge. Our researchgroup succeeded in fabricating suspended GNRs by an advanced plasma CVD process
combining with unique nanobar structures as a catalyst [1-3]. Wafer scale integration of
millions of suspended GNR can be also fabricated with our method [2]. Unfortunately,
however, the on/off current ratio is still distributed in low level (~10) and further
improvement of device performances are required for the practical use of our GNR devices.
In general, the formation of armchair edge structureswith narrow width is required to open the bandgap in
GNRs. This edge control in atomic level requires very hightechnical skills, which is difficult to realize in the wafer
scale. It is theoretically predicted that the potential barrier
can be naturally formed between GNRs junctions(homojunction GNR) independent of edge structures.
However, the accuracy of this prediction and effects ofjunction angle have not been experimentally confirmed yet.
In this study, we attempted to fabricate GNR
homojunction (Fig.1 (a)) with various junction angles and Fig.1 (a) Schematic illustration of
elucidate the correlation between junction structures and GNR homojunction growth withelectrical properties of GNR devices. The GNR plasma CVD from nanobar catalyst.
homojunctions with various junction angles were grown by (b) The distribution of on/off current
ration of GNR homojunction
designing the initial nanobar structures. Various nanobars transistor in various junction angles.
including the contact angle from 60 to 180 º were drawn by
a conventional electron-beam lithography technique. Based on this approaches, GNRs were
found to be grown even from the junction structure of nanobar, indicating the GNR
homojunction devices with various junction angle can be fabricated with our method. Then,on/off current ratio of GNR homojunction device was investigated as a function of junction
angle. It is found that the relatively high on/off can be obtained at the specific junction angle
around 135º (Fig.1 (b)). Although the critical mechanism for arising of this high on/off at
specific junction angle is under investigations, this unique structures may contribute to
opening a new direction for controlling the electrical properties of GNRs.
[1] T. Kato and R. Hatakeyama: Nature Nanotechnology, 7 (2012) 651.
[2] H. Suzuki, T. Kaneko, Y. Shibuta, M. Ohno, Y. Maekawa, and T. Kato: Nature Communications, 7 (2016)
11797.
[3] H. Suzuki, N. Ogura, T. Kaneko, and T. Kato: Scientific Reports 8 (2018) 11819.
Corresponding Author: N. Ogura, Tel: +81-22-795-7046, E-mail: noritada.ogura.p6@dc.tohoku.ac.jp- 23 -

1-8
Electrical monitoring of methane oxidation reaction
using monolayered films of transition-metal oxide nanosheets○Ryo Nouchi1,2, Yoshiaki Ishihara1, Wataru Sugimoto3
1

Department of Physics and Electronics, Osaka Prefecture University, Sakai 599-8570,
Japan
2
PRESTO, Japan Science and Technology Agency, Kawaguchi 332-0012, Japan
3
Research Initiative for Supra-Materials (RISM) and Faculty of Textile Science andTechnology, Shinshu University, Ueda 386-8567, Japan

A change in electrical resistance is a facile platform for monitoring chemical reactions.
However, a reaction-induced change in resistance is usually masked by a high bulk
conductivity of the sensing layer. Thus, an ultrathin sensing layer is desired to enhance thesurface sensitivity. In addition, the sensitivity originates from reactivity and/or catalytic
activity of the sensing layer towards a chemical reaction to be sensed. Therefore, an
atomically thin material that possesses reactivity towards a target chemical reaction should be
employed as the sensing layer to achieve electrical monitoring of the reaction.
Methane (CH4) is the main component of natural gas such as shale gas and now regarded
as an alternative carbon source to petroleum for producing useful chemicals. Oxidation(dehydrogenation) is the first step to produce the chemicals, but CH4 possesses the moststable C–H bond among all hydrocarbons. Thus, a lot of efforts have been devoted to finding
a material that enables facile dehydrogenation of CH4. Recently, Weaver et al. reported thatCH4 undergoes dehydrogenation at low temperatures on a surface of iridium oxide single
crystals [1].
In this study, the electrical monitoring of CH4 oxidation is achieved by employing
monolayered iridium oxide nanosheet films as an atomically thin sensing layer. The nanosheet
films were fabricated on a SiO2/Si substrate by the layer-by-layer method using a nanosheet
suspension [2]. Two types of changes in electrical resistance were observed upon CH4
exposure, depending on the thickness of the sensing
layer: (1) a resistance decrease in a monolayered film
due to (partial) reduction of the iridium oxide
nanosheets (bulk resistivity: IrO2 > Ir [3]) [Fig. 1(a)],and (2) a resistance increase in a thicker film due toincreased surface scattering [4] upon adsorption of
CH4 and/or reaction products [Fig. 1(b)]. The
observation of the resistance decrease with amonolayered film is a verification of the occurrenceof the CH4 oxidation reaction.
[1] Z. Liang, J. F. Weaver et al., Science 356, 299 (2017).
[2] D. Takimoto, W. Sugimoto et al., Electrocatalysis 8, 144(2017).
[3] S.-W. Kim et al., J. Appl. Phys. 103, 023517 (2008).
[4] R. Nouchi and I. Kanno, J. Appl. Phys. 97, 103716 (2005).
Corresponding Author: R. Nouchi
Tel: +81-72-254-8394, Fax: +81-72-254-8394,
E-mail: r-nouchi@pe.osakafu-u.ac.jp- 24 -

Fig. 1 Change in electrical resistance of(a) monolayered and (b) thicker films ofIrO2 nanosheets upon CH4 exposure.

1-9
Mechanical properties of 2D materials, scaling from monolayer tomacroscale○ Dai-Ming Tang 1, Xin Zhou 1, Fengchun Hsia 1, Yoshio Bando 1, Dmitri Golberg 1
1World Premier International Center for Materials Nanoarchitectonics, National Institute forMaterials Science, Namiki 1-1, Tsukuba, Ibaraki 305-0044, Japan
It is essential to understand the mechanical properties of individual and assembled low-dimensional materials for their applications in nanoelectromechanical systems (NEMS),
structural composite materials and some functional materials such as energy storage devices. In
our research, in situ transmission electron microscopy (TEM) method is developed and applied
to measure the mechanical properties of nanostructures and to directly correlate with themicrostructures at multiple length scales. We developed a high-order resonance method toprecisely evaluate the elastic properties of individual nanostructures with the error ~ 1%.1-2
Plastic deformation was realized for individual carbon nanotubes by elongation under Joule
heating, and metal-to-semiconductor transition was realized by modifying the chirality.3
In this talk, I will firstly discuss the bending behaviors of two dimensional (2D) atomic layers
during nanomechanical cleavage,4-5 which was the key process for discovering 2D materials.
In situ observations combined with molecular dynamics simulations reveal layer-dependent
mechanisms, from spontaneous rippling (~5 atomic layers) to homogeneous curving (~10layers) and finally to kinking (20 or more layers). The second part will focus on the size effects
on the mechanical properties of nanoporous graphene networks.6 A strong size effect was
revealed by in situ compression of micro- and nano-pillars inside electron microscopes. Boththe modulus and strength are drastically increased as the specimen size reduces to ~100 nm,
because of the reduced weak links in a small volume. Molecular dynamics simulations reveal
the deformation mechanism involving slip-stick sliding, bending, buckling of graphene sheets,
collapsing and densification of graphene cells.
[1]
[2]
[3]
[4]
[5]
[6]

X. Zhou, D.-M. Tang, et al., Nano Lett 19, 4974 (2019).
F.-C. Hsia, D.-M. Tang, et al., Nanoscale Advances, 10.1039/C8NA00373D (2019).
D.-M. Tang et al., Ultramicroscopy 194, 108 (2018).
I. Nikiforov, D.-M. Tang, et al., Phys Rev Lett 109, 025504 (2012).
D.-M. Tang et al., Nat Commun 5, 3631 (2014).
D.-M. Tang et al., Adv Funct Mater 0, 1900311 (2019).

Corresponding Author: D.-M. Tang
Tel: +81-29-860-4949,
E-mail: Tang.Daiming@nims.go.jp- 25 -

1-10
Long Linear Carbon Chains inside CNT Formed
by Electric Discharge of a SWCNT film
○Yahachi Saito1, Koji Asaka2, Toshiyuki Ishida3
1

Toyota Physical and Chemical Research Institute, Nagakute-city 480-1192, Japan2
Department of Applied Physics, Nagoya University, Nagoya 464-8603, Japan
3
ARS. Inc., Toyohashi 441-8031, Japan

Carbyne, an infinite carbon chain, has attracted much interest and induced significant
controversy for many decades. The presence of long linear carbon chains (LCCs) insidecarbon nanotubes (CNTs) was substantiated in CNT produced by arc-discharge [1], by
high-temperature annealing [2] and X-ray irradiation followed by thermal annealing [3] of alump of CNTs. Last year, we found that long LCCs were encapsulated in CNTs on a film
scale after field emission (FE) experiments of CNT
films [4]. In the present report, an electric dischargethat introduces damage to CNTs is shown to play a keyrole in the formation of LCC@CNT, and additional
findings by Raman spectroscopy are presented.
Thick films of eDIPS CNT (Meijo Nano Carbon)
were used for FE in vacuum and for a target ofhigh-voltage electric discharge in atmosphere. Raman
spectroscopy of the CNT films damaged after discharge
was carried out with a range of excitation photon
energies from 1.58 to 3.49 eV (Fig. 1). Raman bands
at ~1850 cm-1 characteristic of LCCs were observed at
excitation wavelengths from 488, 532, 633, and 671 nm.
The strong resonant Raman scatterings at excitation
photons (1.85 - 2.54 eV) indicate that the energy gaps
of LCCs inside CNTs are distributed in this energy
range.
Transmission electron microscopy (TEM)
revealed the presence of long LCCs within a channel of
CNT (Fig. 2). Not only a single LCC but also two
Fig. 1 Raman spectra.
LCCs in parallel inside a CNT are found.
Acknowledgement: Raman measurement with 671 nm excitation was
conducted by Nanophoton Corp. Prof. T. Wakabayashi for valuable
discussion and Prof. H. Ogata for measuring Raman spectra with 488
and 633 nm excitation are acknowledged. Thanks also to Meijo Nano
Carbon Co. Ltd. for supplying SWCNT mats.
[1] X. Zhao et al, Phys. Rev. Lett. 90 (2003) 187401.
[2] L. Shi et al, Nature Mater. 15 (2016) 634.
[3] T. Murakami, et al., AIP Advances 6 (2016) 085303.
[4] S. Toma, K. Asaka, M. Irita, Y. Saito, Surf. Interface Anal. 51 (2019) 131.
Corresponding Author: Y. Saito
Tel: +81-561-57-9516, Fax: +81-561-63-6302, E-mail: ysaito@toyotariken.jp- 26 -

Fig. 2 TEM image

1-11
Plasma Implantation of Lithium-Ion into Inner Space of C70:
Synthesis and Characterization of Lithium-Ion-Encapsulated C70 (Li+@C70)○Hiroshi Ueno,1,2 Kazuhiko Kawachi,3 Daiki Kitabatake,2 Keijiro Ohshimo,2 Hiroshi Okada,3Eunsang Kwon,4 Shinobu Aoyagi,5 Yasuhiko Kasama,3 Fuminori Misaizu2,61

The Frontier Research Institute for Interdisciplinary Sciences (FRIS), Tohoku University,
Sendai 980-8578, Japan2
Department of Chemistry, Graduate School of Science, Tohoku University,
3
Idea International Co. Ltd.
4
Research and Analytical Center for Giant Molecules, Tohoku University
5
Department of Information and Basic Science, Nagoya City University
6
New Industry Creation Hatchery Center, Tohoku University

Ion-implantation is one of the powerful tools to access endohedral metallofullerenes.
Previously, we have reported an efficient implantation of lithium ion into C60 by using
improved ion-implantation technique, so-called “plasma shower method”.[1,2] This approachallowed us to achieve scalable synthesis of lithium-ion-encapsulated fullerene Li+@C60 X–, astable ionic form of lithium encapsulated fullerene consisting of Li+ inside, neutral C60 cageand external counter anion X–.[3] Despite the unique properties arising from their ionic natures,no other ionic metallofullerenes have been well studied so far.
In this work, mixed fullerene containing C60, C70, and several kinds of higher fullerenes
was used as target of lithium plasma implantation.[4] Laser desorption ionization (LDI) mass
spectrum of the crude product indicated the formation of Li@C60, Li@C70, Li@C76, Li@C78,
and Li@C84 (Figure 1). The
products
werepurifiedaccordingtopreviously
developed oxidative purification
process
followedby[2]
electrolyte-added HPLC. Till
now, scalable amount of
Li+@C70 has been successfully
isolated as TFSI– (TFSI=
bis(trifluoromethanesulfonyl)imi
de) salt. Details of the synthetic
process along with basic Figure 1. (a) Positive mode LDI-TOF mass spectrum ofproperties of Li+@C70 salt will crude product. (b) Expanded view around m/z = 845.
Simulated spectrum of Li@C70 are also shown.
be discussed in the presentation.
[1] Aoyagi, S. et al., Nature Chem. 2010, 2, 678.
[2] Okada, H. et al., RSC Adv. 2012, 2, 10624.
[3] For the difference between Li@C60 and Li+@C60, see Ueno, H. et al., Chem. Sci. 2016, 7, 5770.
[4] Major component of the sample used was estimated by HPLC: C60 (ca. 60%) and C70 (ca. 20%).
Corresponding Author: H. Ueno
Tel: +81-22-795-7645, Fax: +81-22-795-6580, E-mail: hiroshi.ueno.d5@tohoku.ac.jp- 27 -

1-12
The Cage Dependence of Single Molecule Magnet Properties of
Dy-dimetallofullerene Anions○Ryoya Takai1, Ryuji Higashinaka2, Yuji Aoki2, Koichi Kikuchi1,
Yohji Achiba1, Takeshi Kodama1
1

Department of Chemistry, Tokyo Metropolitan University, Tokyo 192-0397, Japan2
Department of Physics, Tokyo Metropolitan University, Tokyo 192-0397, Japan

Since the discovery of single molecule magnet (SMM), SMM has been attracted large
attention due to the expectation to application for high-density storage and quantum computer.
In 2017, Liu et al. reported Dy2@C80(Ih)CH2Ph has over 3000 s of the relaxation time ofmagnetization at low temperature[1]. On the other hand, in 2019, Velkos et al. theoreticallycalculated the intra-cage electrostatic potentials for C80(Ih), C80(Ih)CH2Ph, and C79N, andpointed out the different potentials would lead to the different SMM properties[2].
In the previous symposium[3], we reported the isolation of [Dy2@C78(D3h)]- and[Dy2@C80(Ih)]-. In this work, to elucidate SMM properties of them, we measured M-T curve,
M-H curve, and relaxation time (τm) of magnetization.
The τm vs 1/T plots for [Dy2@C78(D3h)]- and [Dy2@C80(Ih)]- are shown in Fig. 1. The fit
function of τm is eq. (1). The first, the second, and the last terms represent quantum tunneling,
Raman, and Orbach processes, respectively.

τm-1 = τQTM -1 + CT n + τ0 -1 exp(-Ueff/T)

(1)

-

-

Fig. 1 τm vs 1/T plots for (left) [Dy2@C 78(D3h)] and (right) [Dy2@C 80(Ih)]

The obtained parameters, τQTM and Ueff, are listed in Table 1. Comparing the results
obtained in the present work between C78(D3h) and C80(Ih), we can easily notice that both τQTM
and Ueff are largely different. On the other hand, Ueff of C80(Ih) and C80(Ih)CH2Ph is almost
identical but τQTM is different.
Table 1 τQTM and Ueff

τQTM/sUeff/K[Dy2@C78(D3h)]-[Dy2@C80(Ih)]-

170
176

5438
606

Dy2@C80(Ih)CH2Ph[ref. 1]3257
613

[1] F. Liu et al., Nat. Commun. 8, 16098(2017).
[2] G. Velkos et al., Angew. Chem. Int. Ed. 58, 5891(2019).
[3] R. Takai et al., The 55th Fullerenes-Nanotubes-Graphene General Symposium 127(2018).
Corresponding Author: Takeshi Kodama
Tell: +81-42-677-2530, Fax: +81-42-677-2525
E-mail: kodama-takeshi@tmu.ac.jp- 28 -

1-13
Development of Mobility, Charge and Optical Measurement System for Nanomaterials○Toshiki Sugai, Fumiaki Uchiyama, Yuya Ooishi, Reona Miyamoto, Ryo Sasaki, Takanori
Nakayasu, Kanata Oguri, and Tomoya Ono
Department of Chemistry, Toho University, Miyama 2-2-1 Funabashi, 274-8510, Japan
Ion mobility spectrometry (IMS) combined with mass spectrometry has revealed novel
information on nanomaterials such as fullerenes[1]. However, the sizes of nanomaterials havebeen growing wider and wider from carbon nanotubes to graphene for example. Thesematerials cannot be detected mass spectrometry so other measurement systems should be
combined with IMS to study them. We also have been working on nanocarbon materials suchas graphene quantum dots with our newly developed IMS combined with ion trap and opticalmeasurement system. Even with the new system it is still difficult to clarify their structures
because mobility observed by IMS depends on both of structures and charges of samples. To
overcome this difficulty, here we present
simultaneous mobility, charge, and opticalmeasurement system.
The system consists of an electrospray ion
source (ESI) for production of positively
charged nanodroplets, a trap type IMS, anda charge detector. Charged droplets were
produced and trapped in the IMS system
Fig. 1 Charge and Drift Time Profile ofunder ambient condition. Then the droplets
Nanodroplets
were drifted around several cm, and thenwere detected by the charge detector. Figure
1 shows the detected charge and drift time profile of the droplets. The horizontal axis shows
the drift time and the vertical axis shows the amount of the charge. From those peaks of the
profile, the size around 100 nm and charge around thousands of e were identified, which isconsistent with ESI condition. This system can be applied general nanomaterials with opticalmeasurements.

[1] G. von Helden et al., J. Chem. Phys., 95, 3835 (1991).

TEL: +81-47-472-4406, E-mail: sugai@chem.sci.toho-u.ac.jp- 29 -

2-1
One dimensional characteristics in thermoelectric properties ofsemiconducting single walled carbon nanotubes
Yota Ichinose1, Kan Ueji1, Yohei Yomogida1, Kazuhiro Yanagi1
1Department of Physics, Tokyo Metropolitan University, Hachioji Tokyo 192-0397, Japan

Thermoelecrics are a very important technology for efficient conversion of waste heat toelectrical power. Theoretical studies have suggested that lowering dimensionality can enhancethermoelectric performance due to the following two factors, (1) quantum confinement effectand (2) reduction of thermal conductivity.1 Enhancement of thermoelectric performance byreduction of thermal conductivity is well confirmed, but experimental clarification on how the
low-dimensional electronic structure can enhance thermoelectric performance has been
elusive. Single walled carbon nanotubes (SWCNTs) are a very good model for studying
relationships between one-dimensional electric structure and thermoelectric properties. Our
recent study revealed unique one-dimensional characteristics in their thermoelectric
properties.2 For example, in conventional metallic materials, the increase of their conductivity
induces the decrease of their Seebeck coefficient, which is called as thermoelectric trade-off.
However, in the case of metallic SWCNTs, the trade-off is violated. In metallic SWCNTs, we
can observe enhancement of both Seebeck coefficientand conductivity because of the presence of van-Hove
singularity (vHs) in density of states, reflecting 1Delectronic structure. In the case of semiconducting
SWCNTs, however, it has been very difficult to discuss
1D characteristics in their thermoelectric properties. We
cannot distinguish three, two or one-dimensional
characteristics in the line-shapes of Seebeck coefficientsas a function of Fermi-level in semiconductor materials.
However, a recent theoretical study pointed out theimportance of thermoelectrical conductivity.3 Only inthe case of 1D materials, a sharp peak structure can beobserved around 1st vHs in thermoelectrical conductivity.
Thus, in this study, we investigated the thermoelectricalconductivity of semiconducting SWCNTs with various
chiralities.
Figure1showsthermoelectricalconductivities as a function of gate voltages insemiconducting SWCNTs with various chiralities. When
we prepare (6,5) SWCNTs with purity more than 99%,
we could observe a sharp peak structure inthermoelectrical conductivity. This sharp peak structure Fig1. Thermoelectric conductivity,in thermoelectrical conductivity clearly reflects vHs the L12 term, of (6,5), (9,4), (10,3)
structure. In this talk, we will discuss the background.
andSemi(semiconducting
SWCNT with diameter of 1.4 nm)
References: [1] Hicks&Dresselhaus,PRB 47, 16631 as a function of gate voltage.
(1993) [2] Ichinose et al., Nano Lett. 19, 7370 (2019) [3]Yamamoto & Fukuyama, JPSJ 87, 114710 (2018)
Corresponding Author: K. Yanagi, E-mail: yanagi-kazuhiro@tmu.ac.jp- 30 -

2-2
Synthesis of Boron Nitride Nanotubes and MoS2@BNNTs Heteronanotubes○ Ming Liu1, Yongjia Zheng1, Yang Qian1, Rong Xiang1, Taiki Inoue1, Shohei Chiashi1, Esko
I. Kauppinen2, Shigeo Maruyama1,3*
1

Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan2
Department of Applied Physics, Aalto University School of Science, PO Box 15100,
FI-00076 Aalto, Finland
3
Energy NanoEngineering Lab., National Institute of Advanced Industrial Science andTechnology (AIST), Tsukuba 305-8564, Japan

Inorganic nanotubes have initiated a surge of intensive research in the last few years since
the discovery of tungsten disulphide nanotubes in 1992 [1]. Lately, MoS2 nanotubes [2] havebeen started to be produced in decent amounts and with promising potentials for large scale
application, mostly as superior solid lubricants and in nanocomposites. The synthesis ofsingle-walled MoS2 nanotubes is still a challenge in the field, however, due to a combined
theoretical and experimental work indicated that multiwall MoS2 nanotubes with inner corelarger than 6 nm are more stable than single-walled nanotubes [3]. Moreover, a boron nitride
nanotube (BNNT), a structural analogue of a carbon nanotube in nature, is an electricalinsulator with a bandgap of ca. 5.5 eV, basically independent of tube chirality andmorphology.
In this work, firstly, we present a template-assisted synthesis method for producing highquality and single crystalline BNNTs via a CVD coating BN on pristine single-walled carbon
nanotubes and subsequent removal of the template. The coating method of synthesizing
coaxial nanotubes of single walled carbon nanotubes and BNNTs is recently developed in ourgroup [4]. The quality and crystalline structure of BNNTs are examined by TEM and Raman
spectroscopy characterizations (Figure 1 (a)). The optical bandgap of as-synthesized BNNTs
is proven as 5.76 eV by absorption spectra. Moreover, we also demonstrate a facile CVD
process of producing a hetero nanotube structure of combining MoS2 nanotubes and BNNTs(MoS2@BNNTs), as shown in Figure 1(b). BNNTs provides a wide cavity for a layered MoS2
to fit into the core and enfold within it to form a tubes, as well as serves as an optically andelectrically passive template for investigating the optical properties of single-walled MoS2
nanotubes. The comparison of Raman
spectra and PL spectra between
multi-walled and single-walled MoS2
nanotubes is discussed in this work.
[1] R. Tenne et al. Nature 360, 444 (1992).
[2] Y. Feldman et al. Science 267, 222 (1995).
[3] G. Seifert et al. J. Phys. Chem. B 106, 2497
(2002).
[4] R. Xiang et al. arXiv: 1807.06154 (2019).
Figure 1 (a) Representative Raman spectrum and TEM
Corresponding Author: Shigeo Maruyama
Tel: +81-3-5841-6421
E-mail: maruyama@photon.t.u-tokyo.ac.jp

image of BNNTs. (b) Representative TEM image andatomic model of MoS2@BNNTs.

- 31 -

2-3
Influence of interlayer stacking on gate-induced carrier accumulation in avan der Waals heterostructure comprising MoS2 and WS2○Mina Maruyama, Susumu Okada
Department of Physics, Graduate School of Pure and Applied Sciences, University of Tsukuba,
Tsukuba 305-8571, Japan
Transition metal dichalcogenides (TMDCs) are regarded as channel materials of field
effect transistors (FET) because of their semiconducting electronic properties and chemicallyinert sheet structure. In addition, TMDCs can form van der Waals (vdW) heterostructures
which exhibit interesting variations in their electronic structures depending on the electronic
band structures of constituent layers and interlayer interaction. Accordingly, asymmetriccarrier accumulation occurs in the vdW heterostructure comprising MoS2 and WS2, owing to
its type-II band-offset [1]. We further demonstrated similar asymmetric carrier doping inbilayer MoS2 in dual gate FET by controlling perpendicular electric field and carrier
concentration. Thus, in the present work, we aim to investigate the influence of band offset
and the electric field on carrier accumulation in bilayer MoS2/WS2 FET, using density
functional theory with effective screening medium method. To simulate the bilayer
MoS2/WS2-FET, we consider the structural model shown in Fig. 1 where the MoS2/WS2 issandwiched by top and bottom gate electrodes which are
simulated by effective screening medium with infinite
dielectric constant.
Our calculations showed that carrier distribution in
MoS2/WS2 is sensitive to field direction, field strength,
carrier concentration, and interlayer stacking arrangement(Table I). Under the electric field whose direction enhances
the band offset, the electron localization in MoS2 layer
increases with increasing the field strength. On the contrary,electron is spilled over WS2 layer with the increase of the
field whose direction suppresses the band offset. The
electron localization is substantially suppressed by
Structural model ofFig.1
increasing the electron concentration. We further found thatbilayer MoS2/WS2–FET with
the interlayer stacking misorientation causes the
top and bottom gate electrodes.
enhancement of electron accumulation in MoS2 layer owing
to the decease of the interlayer interaction.
Table 1. Carrier distribution in bilayer WS2/MoS2 (AB stacking) under an electric field.

-1.0 V/nm-0.1 V/nm

0.1 V/nm

1.0 V/nm

W/Mo

W/Mo

W/Mo

W/Mo

1013 e/cm2

45%/55%36%/64%34%/66%27%/73%1014 e/cm2

47%/53%

43%/57%42%/58%38%/62%[1] M. Maruyama and S. Okada, Appl. Phys. Express 12, 075008 (2019).
Corresponding Author: M. Maruyama
Tel: +81-29-853-5921, Fax: +81-29-853-5924, E-mail: mmaruyama@comas.frsc.tsukuba.ac.jp- 32 -

2-4
First-principles electronic-structure study ofstabilities and electronic properties of trilayer h-BN
○Taishi Haga1, Yuuto Matsuura1, Yoshitaka Fujimoto1, and Susumu Saito1,2,3
Department of Physics, Tokyo Institute of Technology, Tokyo 152-8551, Japan
Advanced Research Center for Quantum Physics and Nanoscience, Tokyo Institute ofTechnology, Tokyo 152-8551, Japan
3
Materials Research Center for Element Strategy, Tokyo Institute of Technology,
Kanagawa 226-8503, Japan
1

2

Hexagonal boron nitride (h-BN) thin layers as well as its bulk phase attract much attention
as not only substrate but also future wide-gap semiconductor materials. Unlike graphene witha sixfold symmetry, the h-BN layer has only a threefold symmetry, and they accordingly havedifferent stacking directions. Therefore, in h-BN multilayer systems, there are many more
possible stacking sequences than in the graphene multilayer. Hence, various electronic
properties of h-BN layers depending on its stacking sequence should appear. Actually, it has
been reported that h-BN bilayers show various electronic properties depending on theirstacking sequences [1]. Defects in semiconductors often play a key role to modify anddetermine the electronic properties of the system. Therefore, it is important to theoreticallystudy how an impurity in h-BN affects the electronic properties. In the present work, we study
stabilities and electronic structure of h-BN trilayers using first-principles electronic-structure
calculations within the framework of the density functional theory. It is found that the relative
donor and acceptor ionization energies depend on the stacking sequence [2]. It is also foundthat spatial distributions of the valence band top and conduction band bottom states can belocalized in specific h-BN layer. By using this result, we design the C-doped h-BN trilayerthat allows modulation doping [Fig. 1].

Figure 1 Spatial distributions of the impurity-induced states and the valence-band-top statesof the abc-stacked h-BN trilayer. The top h-BN layer is doped with C atom at the N site. The
doped layer and the carrier conductive layer are separated from each other.
[1] Y. Fujimoto, and S. Saito, Phys. Rev. B 94, 245427 (2016).
[2] T. Haga, Y. Matsuura, Y. Fujimoto, and S. Saito, to be published.
Corresponding Author: T. Haga
E-mail: haga.t@stat.phys.titech.ac.jp- 33 -

2-5
Molecular modification of graphene/Au electrode forcontrolled proton permeability○Tomohiro Fukushima, Takaha Komai, Hidetaka Hasebe, Kei Murakoshi
Department of Chemistry, Faculty of Science, Hokkaido University,
Sapporo, 060-0810, Japan- 34 -

2500

1580

ω2D / cm-1

[1] T. Fukushima, K. Murakoshi, Current Opinion in Electrochemistry,
17, 158 (2019).
[2] M. Lozada-Hidalgo, H. A. Wu, A. K. Geim et al., Nature 516, 227(2014).
Corresponding Author: K. Murakoshi
Tel: +81-11-706-2704, Fax: +81-11-706-4810,
E-mail: kei@sci.hokudai.ac.jp

ωG / cm-1

Intensity / cps

Current density / µA cm-2

The electronic and chemical properties of graphene can be modulated through the interfacialinteraction.[1] Recently, Geim et al., reported that graphene can be uniquely used as proton
permeable membrane.[2] The control of the proton permeability can be useful for theapplications such as the separator for electrochemical systems. However, it is still difficult tocontrol the structure of graphene. Here, we show that molecular modification of graphenesurface can modulate the proton permeability from in-situ Raman spectroscopy underelectrochemical potential control.
We prepared Au (111) surface through the Cavalier300
method, and graphene was prepared through the chemical
vapor deposition. Molecular modification of graphene was200
accomplished by the electrochemical oxidation ofphenylhydrazine
derivatives.
Electrochemical
100
measurements were conducted in 0.1 M NaClO4 in thepresence of 2 mM phenylhydrizene as shown in Figure 1. In
0
-0.2
0.0
0.2
0.4
0.6
the absence of phenylhydrazine, anodic current was not
Potential / V vs. Ag/AgCl
observed. On the other hand, in the presence ofphenylhydrazine, anodic current was observed from -0.2 V Figure 1. Cyclic voltammogram of G/Au in the(black)andpresenceofvs. Ag/AgCl. The anodic feature was different from second absence
phenylhydrazine (red) in 0.1 M NaClO4.
cycle suggesting that deposition of phenyl groups on G/Au Sweep rate: 50 mV/s.
electrode (Ph-G/Au). Figure 2 shows the Raman spectra of
G/Au and Ph-G/Au. G band (1580 cm-1) and 2D band (2700
10 cpscm-1) were observed for the as-prepared G/Au electrode. On
the other hand, D band (1350 cm-1) was additionallyobserved for Ph-G/Au. Raman spectroscopy revealed thatsuccessful modification of graphene surface byphenylhydrazine. Figure 3 shows the electrochemical
1000
1500
2000
2500
3000
-1
Raman
shift
/
cm
potential-dependent G band and 2D band position of G/Au
electrode. G band and 2D band remains similar position. 2D Figure 2. Raman spectra of G/Au (black)and Ph-G/Au (red) (514 nm, 0.5 mW).
band suddenly droped at -1.9 V and reversibly. The observed
1620
2D band shift is due to the intercalation of H2 molecules
2700
between graphene and Au through the proton tunneling.
1600
Effect of molecular modification will be discussed.
2600

2400
1560
-2.0

-1.5 -1.0 -0.5
0.0
Potential / V vs. Ag/AgCl

Figure 3. G band (black) and 2D band (red)peak position of G/Au electrode.

3-1
Carbon nanotube-based excitonic wavelength-selective absorber andemitter for solar thermal energy harvesting○Yuhei Miyauchi1, Taishi Nishihara1, Akira Takakura1, Kazunari Matsuda1, Takeshi Tanaka2,and Hiromichi Kataura2
1
2

Institute of Advanced Energy, Kyoto University, Uji, Kyoto 611-0011, Japan.
Nanomaterials Research Institute, AIST, Tsukuba, Ibaraki 305-8565, Japan.

Technologies for solar energy harvesting have been of central importance in society overrecent years because their developments are considered as the key to conquer the urgent social
requirement for reducing CO2 emission on a global scale. In addition to solar photovoltaics(PV), utilization/management technologies of solar thermal energy have been of strong
interest because of their high thermodynamic energy conversion efficiency and low cost. Oneof the key components in solar thermal technologies is a device with wavelength-controlled
absorptivity/emissivity, called selective absorber/emitter. A pair of selective absorber andemitter is used for spectrally shaping the broadband solar spectrum into a narrow-bandnear-infrared thermal radiation, which can be used as an input to a semiconductor PV cell toefficiently generate electricity; this scheme is called solar thermophotovoltaics (STPV).
Owing to the reduced thermalization loss in the PV cell, if an ideal selective absorber/emitter
pair is available, STPV has a very high principle energy conversion efficiency of more than
60 %, which far exceeds the Shockley–Queisser limit of a standard Si solar cell (~ 30 % [1]).
Thus, STPV has attracted growing attention as an emerging concept of the solar energy
harvesting. However, the reported conversion efficiency of the state-of-the-art STPV (< 10 %[2]) is still much lower than the principle efficiency, partially due to non-ideality of therealistic selective absorber/emitter pairs.
Here, we demonstrate application of single-chirality enriched semiconducting single-walledcarbon nanotubes (SWNTs) for the selective absorbers and emitters with an excellent
wavelength tunability via selection of the SWNT chirality. Optical spectra of semiconducting
SWNTs are dominated by thermally stable excitons whose resonant wavelengths depend on
the chirality of SWNTs, and excitonic spectra are stable even at elevated temperatures morethan 2000 K [3] owing to the large binding energy of one-dimensional excitons. This uniqueexciton property provides an excellent tunability of the wavelength cut off of the absorbercomposed of chirality-selected SWNTs. Moreover, thermal radiation with very narrowspectral bandwidth arising from thermal generation and radiative recombination of excitons isavailable [3], which offers an ideal thermal optical property as a selective emitter. We will
discuss the thermal and optical characteristics of the macroscopic selective absorber/emitter
thin films fabricated using single-chirality enriched SWNTs [4].
[1] W. Shockley and H. J. Queisser, J. Appl. Phys. 32, 510 (1961).
[2] D. M. Bierman, A. Lenert, W. R. Chan, B. Bhatia, I. Celanović, M. Soljačić, and E. N. Wang, Nat. Energy 1,
16068 (2016).
[3] T. Nishihara, A. Takakura, Y. Miyauchi, and K. Itami, Nat. Commun. 9, 3144 (2018).
[4] Y. Yomogida, T. Tanaka, M. Zhang, M. Yudasaka, X. Wei, and H. Kataura, Nat. Commun. 7, 12056 (2016).
Corresponding Author: Y. Miyauchi
Tel: +81-774-38-3463
E-mail: miyauchi@iae.kyoto-u.ac.jp- 35 -

3-2
Machine-learned 100 %-yield carbon nanotube dissolution in arbitraryorganic solvents○Yoshiyuki Nonoguchi1,2, Tomoyuki Miyao1,3, Chigusa Goto1, Tomoko Murayama1, Kimito
Funatsu1,3,4, Tsuyoshi Kawai1
1

Division of Materials Science, Nara Institute of Science and Technology, Ikoma 630-0192,
Japan
2
JST, PRESTO, Kawaguchi 332-0012, Japan
3
Data Science Center, Nara Institute of Science and Technology, Ikoma 630-0192, Japan
4
Department of Chemical System Engineering, School of Engineering, The University ofTokyo, Tokyo 113-8656, Japan

The insolubility of single-walled carbon nanotubes (SWCNTs) into organic solvents has
been a common sense except for the uses of aqueous amphiphilic surfactant systems and a
few magic solvents such as N-cyclohexylpyrrolidone [1,2]. Despite tremendous practicalrequirements, the preparation of organic SWCNT inks with complete homogeneity and longshelf time is rarely allowed. Few successful organic inks include dispersions with conducting
polymers and polyvinyl ketone in nonpolar solvents. In order to make the inks with more
arbitrary, more practical, and more preferred organic solvents, the understanding of
SWCNT-surfactant-solvent interactions is indispensable.
This work demonstrates the surfactant-assisted,high yield dissolution of SWCNTs in ordinary organic
solvents including alcohol, ketone, ester and ether.
The surfactants used here are commercially available
acid-base pairing compounds, where the polarity ofdispersing solvents is apparently associated withsurfactant ionicity. Representatively, cellulose
derivatives such as ethyl cellulose enabled theefficient dissolution of SWCNTs in organic solvents(Fig. 1A). A feature extraction based on themultivariate analysis and genetic algorithm reveals
seemingly important physicochemical requirements
for the efficient dissolution (Fig. 1B). These
elucidated factors are associated with not only
solvents-surfactant, but also solvent-SWCNT
interactions. The free and universalized SWCNT
dispersion design described here will lay thegroundwork for many applications ranging fromfundamental
nanofluidics
tosolution-based
fabrication.
Fig. 1 (A) Dispersion of SWCNTs in
THF with the aid of ethyl cellulose.
(B) Cross-validation analysis of
SWCNT solubility in 81 solvents
examined using S22 absorption.

[1] M. J. O'Connell, et al. Science 297, 593 (2002).
[2] S. D. Bergin, et al. ACS Nano 3, 2340 (2009).
Corresponding Author: Y. Nonoguchi
Tel: +81-743-72-6028, Fax: +81-743-72-6179
E-mail: nonoguchi@ms.naist,jp- 36 -

3-3
Multiscale hydrophobic interactions between gel, SWCNTs, andsurfactants: detailed discussions
Guowei Wang, Takeshi Tanaka, ○Hiromichi Kataura
Nanomaterials Research Institute, AIST, Tsukuba, Ibaraki 305-8565, Japan
We have enjoyed adsorption chromatography for structure sorting of single-wall carbon
nanotubes (SWCNTs), for long time. In this method, semiconducting (S-) SWCNTs are
selectively adsorbed in polysaccharide gels when we used sodium dodecyl sulfate (SDS) for
individually dispersing SWCNTs in water. Furthermore, diameter selective elution process
can be realized diameter sorting of S-SWCNTs. In this method, we expected that thehydrophobic surfaces in polymer network in the gel work as effective adsorption sites for
S-SWCNTs, because such gels have no apparent interactions to analyte except hydrophobic
interactions. However, detailed adsorption mechanism was not well understood. In theprevious presentation, we claimed multiscale hydrophobic interactions can explain theadsorption of S-SWCNTs to the gel. Where, the "wet-dry transition" is mesoscopichydrophobic interaction and surfactant adsorption to SWCNTs is nanoscale hydrophobic
interaction. If the mesoscopic interaction is more stable, SWCNTs can be adsorbed in the gelby removing surfactant molecules from the surface. This is the mechanism of the selective
adsorption of S-SWCNT to the gels. In this presentation, we will try to discuss this interesting
phenomenon by introducing "excluded water volume" as a scale of free energy gain in thehydrogen bonding system without theoretical calculations. Excluded water volume bysurfactant is estimated from the number of surfactants on the surface of SWCNTs, which
depends on the electronic structure of
the SWCNT [1]. The other excluded
water volume can be estimated fromthe gel volume of the adsorption site.
This model clearly explains why thedry state, in which SWCNTs are
directly adsorbed in gels, is stable
when the adsorption site is large
enough (mesoscopic). Furthermore,
our model suggests that similar
mechanisms will be seen everywhere
when we handle nano materials withhydrophobic surfaces.
This work was supported by JST CREST, Grant Nos. JPMJCR16Q2 and JPMJCR18I5,
Japan.
[1] M. Ohfuchi, J. Phys. Chem. C 2018, 122, 4691-4697.
Corresponding Author: Hiromichi Kataura
Tel: +81-29-861-2551
E-mail: h-kataura@aist.go.jp- 37 -

3-4
Enhanced intrinsic photovoltaic effect in tungsten disulfide nanotubes○Yijin Zhang1,2,*, Toshiya Ideue3, Masaru Onga, Feng Qin, Ryuji Suzuki, Alla Zak, Reshef
Tenne, Jurgen H. Smet, Yoshihiro Iwasa 1
1

The Institute of Science and Industrial Research, Osaka University, Osaka 567-0047, Japan
2
Max Planck Institute for Solid State Research, Stuttgart 70569, Germany
3
Department of Applied Physics, The University of Tokyo, Tokyo 113-8656, Japan
4
Faculty of Sciences, HIT-Holon Institute of Technology, Holon 5810201, Israel
5
Department of Materials and Interfaces, Weizmann Institute of Science, Rehovot, Israel
6
RIKEN Center for Emergent Matter Science (CEMS), Wako 351-0198, Japan

Transition metal dichalcogenides (TMDs) such as tungsten disulphide (WS2) arerepresentative 2D materials. One of their unique features is the controllability of the crystal
symmetry. The unit cell of the centrosymmetric bulk TMD is represented by two layers (Fig.
1). Since the inversion centre is located at the wan der Waals gap, isolation of a monolayerfrom bulk crystal naturally breaks the inversion symmetry. When the 2D sheets are rolled up
to form a tubular structure, the mirror and rotational symmetries are broken as well. SuchTMD nanotubes can be synthesized chemically. Most of them are multiwall nanotube with apolar structure [1].

Fig.1 Crystal structures of TMD bilayer (left), monolayer (middle), and nanotube (right).

In this study, we fabricated two metal contacts at ends of an individual multiwall WS2
nanotube and studied the electrical response upon light irradiation. We observed a sizable
photovoltaic effect from intrinsic WS2 nanotubes without formation of a p-n junction, while
such effect was negligibly small in devices out of monolayer and bilayer 2D WS2 flakes [2].
This difference indicates the importance of symmetry breaking for enhancing the photovoltaic
effect occurring in intrinsic materials.
[1] F. Qin et al. Nature Commun. 8, 14465 (2017).
[2] Y. J. Zhang, et al. Nature 570, 349-353 (2019).
Corresponding Author: Y. J. Zhang
Tel: +81-3-5452-6158, Fax: +81-3-5452-6157,
E-mail: yzhang@iis.u-tokyo.ac.jp*Present address: Institute of Industrial Science, The University of Tokyo, Tokyo 153-8505, Japan- 38 -

3-5
Radiative quantum efficiency of bright excitons in carbon nanotubes○H. Machiya1,2, A. Ishii1,3, Y. K. Kato1,3
1

Nanoscale Quantum Photonics Laboratory, RIKEN Cluster for Pioneering Research,
Saitama 351-0198, Japan2
Department of Electrical Engineering, The University of Tokyo, Tokyo 113-8656, Japan
3
Quantum Optoelectronics Research Team, RIKEN Center for Advanced Photonics, Saitama
351-0198, Japan
Carbon nanotubes have potential applications as telecom-band single-photon emitters at room
temperature, and coupling to microcavities can further improve the performance through the
Purcell effect that accelerates the radiative decay into the cavity mode [1,2,3]. One of the key
physical quantity in this process is the radiative quantum efficiency, or the fraction of photons
emitted from excitons. The accelerated decay can be directly observed in the time domain if
the radiative quantum efficiency is high enough, and this behavior allows for determination of
the radiative quantum efficiency without the need to deconvolve the exciton generation
efficiency from the photoluminescence (PL) quantum yield.
Here we experimentally determine the radiative quantum efficiency of bright
excitons in carbon nanotubes [4]. Utilizing ultralow-mode-volume air-mode cavities, theradiative decay rates are enhanced through the Purcell effect. Time-resolved PL measurements
are used to probe the overall decay process including the non-radiative paths, and we observe
PL decay rates accelerated by as much as 3 times compared to typical uncoupled
air-suspended nanotubes [5]. We further analyze the PL spectra by Monte-Carlo simulation of
the cavity-enhanced dynamics of the exciton, extracting the Purcell factors in these devices.
Combining the results from time-domain and spectral-domain measurements, we find that theradiative quantum efficiency of the bright exciton is unexpectedly high.
Work supported in part by RIKEN (Incentive Research Projects), MIC (SCOPE
191503001), JSPS (KAKENHI JP16H05962) and MEXT (Nanotechnology Platform). H.M.
is supported by JSPS Research Fellowship. We thank the Advanced Manufacturing Support
Team at RIKEN for technical assistance.
[1] R. Miura, S. Imamura, R. Ohta, A. Ishii, X. Liu, T. Shimada, S. Iwamoto, Y. Arakawa, Y. K. Kato,Nat. Commun. 5, 5580 (2014).
[2] A. Jeantet, Y. Chassagneux, C. Raynaud, P. Roussignol, J. S. Lauret, B. Besga, J. Estève, J. Reichel,
C. Voisin, Phys. Rev. Lett. 116, 247402 (2016).
[3] A. Ishii, X. He, N. F. Hartmann, H. Machiya, H. Htoon, S. K. Doorn, Y. K. Kato, Nano Lett. 18, 3873
(2018).
[4] H. Machiya, A. Ishii, Y. K. Kato, in preparation.
[5] A. Ishii, H. Machiya, Y. K. Kato, Phys. Rev. X. 9, 041048 (2019).
Corresponding Author: Y. K. Kato
Tel: +81-48-462-1449
Web: http://katogroup.riken.jp/ E-mail: yuichiro.kato@riken.jp- 39 -

3-6
Vapor-Phase Functionalization of Air-Suspended Single-Walled Carbon
Nanotubes Using an Aryl-Halide○Daichi Kozawa1, Xiaojian Wu2, Akihiro Ishii1,3, Jacob Fortner2, Keigo Otsuka3, Rong
Xiang4, Taiki Inoue4, Shigeo Maruyama4,5, YuHuang Wang2,6, Yuichiro K. Kato1,3
1

Quantum Optoelectronics Research Team, RIKEN Center for Advanced Photonics, Saitama
351-0198, Japan2
Department of Chemistry and Biochemistry, University of Maryland, College Park,
Maryland 20742, United States
3
Nanoscale Quantum Photonics Laboratory, RIKEN Cluster for Pioneering Research,
Saitama 351-0198, Japan
4
Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan
5
Energy NanoEngineering Laboratory, National Institute of Advanced Industrial Science andTechnology (AIST), Ibaraki 305-8564, Japan
6
Maryland NanoCenter, University of Maryland, College Park, Maryland 20742 UnitedStatesColor centers in single-walled carbon nanotubes attract interest because of theirsingle-photon emission at room temperature in the telecom range [1, 2]. However, the lack ofvapor-phase reaction route for forming color centers hinders the use of the excellent opticalproperties of air-suspended carbon nanotubes. We herein demonstrate the functionalization of
air-suspended carbon nanotubes using iodobenzene as a precursor. The chemical reaction
procedure is rationally designed to maintain the suspended structure and fluorescent
properties of carbon nanotubes. The formed phenyl group serves as a color center and exhibits
localized exciton emission peaks E11* and E11*- in addition to the free exciton emission peakE11. We characterize over 12 different chiralities, covering nanotubes with diameters d ranging
from 0.981 to 1.29 nm, to elucidate the reactivity and optical property of the color centers. We
find that the reactivity of iodobenzene scales as 1/d, where the inherent strain on the curvatureof nanotubes promotes the reaction. The trapping potential of E11* and E11*- are both close to
the singlet-triplet splitting. The minimum value of g(2)(0) in the photon correlation verifies thephoton antibunching at the color centers. These findings should lead to further developmentof quantum photon sources that utilize color centers in carbon nanotubes.
This work was supported in part by RIKEN (Special Postdoctoral Researcher Program,
Incentive Research Projects), MIC (SCOPE 191503001), JSPS (KAKENHI JP15H05760,
JP16H05962, JP18H05329), and MEXT (Nanotechnology Platform). We thank the Advanced
Manufacturing Support Team at RIKEN for technical assistance.
[1] A. Ishii, X. He, N. F. Hartmann, H. Machiya, H. Htoon, S. K. Doorn, and Y. K. Kato, Nano Lett. 18, 3873
(2018).
[2] X. He, N. F. Hartmann, X. Ma, Y. Kim, R. Ihly, J. L. Blackburn, W. Gao, J. Kono, Y. Yomogida, A. Hirano,
T. Tanaka, H. Kataura, H. Htoon, and S. K. Doorn, Nat. Photonics 11, 577 (2017).
Tel: +81-48-462-1449
E-mail: yuichiro.kato@riken.jp- 40 -

3-7
Atomistic Structural Analysis of Reaction Intermediates Captured on
Functionalized Carbon Nanohorns○Koji Harano1, Junfei Xing1, Luca Schweighauser1, Satoshi Okada1, Eiichi Nakamura1
1

Department of Chemistry, The University of Tokyo, Tokyo 113-0033, Japan

Chemical reactions in solution almost always take place via a series of minute intermediatesthat are often in rapid equilibrium with each other, and hence hardly characterizable at the levelof atomistic molecular structures. We found that single-molecule atomic-resolution real-timeelectron microscopic (SMART-EM) video imaging [1] provides a unique methodology for
capturing and analyzing the minute reaction intermediates, as illustrated here for the isolation,
characterization, and semi-statistical analysis of single prenucleation clusters (PNCs) in thereaction mixture of crystallization of metal–organic frameworks (MOFs) by using
functionalized carbon nanohorns[2]. Specifically, we found two
different types of PNCs are involvedin the formation of MOF-2 andMOF-5 from a mixture of zinc
nitrate and benzene dicarboxylates
in DMF at 95 °C and 120 °C,
respectively [3].
SMART-EM
identified many 1-nm-sized PNCs,
among which a small amount ofcube and cube-like clusters are
involved in the MOF-5 synthesis,
but not in the MOF-2 synthesis. In
the latter, we instead found only
linear and square PNCs, whichsuggestthat
the
MOF-2/-5
bifurcation takes place at the PNC
stage. Such a dataset is uniquely
available by the use of the ‘fishing’strategy, combined with the TEM
video imaging, and highlight the Fig.1 SMART-EM video imaging of PNCs in MOF-2 andpotential of the SMART-EM MOF-5 syntheses from Zn2+ and benzene dicarboxylates.
technology in the study of the TEM images of a cubic PNC of I-MOF-5 (X = I) captured
mechanisms of chemical reactions in on carbon nanohorn with a carboxylate moiety are shown.
solution.
[1] E. Nakamura, Acc. Chem. Res. 50, 1281 (2017).
[2] J. Xing, L. Schweighauser, S. Okada, K. Harano, E. Nakamura, Nat. Commun. 10, 3608 (2019).
[3] L. Schweighauser, K. Harano, E. Nakamura, Inorg. Chem. Commun. 84, 1 (2017).
Corresponding Authors: K. Harano and E. Nakamura
Tel: +81-3-5841-4369, Fax: +81-3-5841-4367
E-mail: harano@chem.s.u-tokyo.ac.jp- 41 -

3-8
Independent degrees of freedom in two-dimensional materials
Sake Wang, F. R. Pratama, M. Shoufie Ukhtary, Riichiro Saito
Department of Physics, Tohoku University, Sendai 980-8578, Japan
Future semiconductor industry that utilizes the intrinsic degrees of freedom (DOFs) ofelectrons has been proved superior to their conventional counterpart, which depends
thoroughly on energy-consuming charge. The three DOFs in two-dimensional (2D) materials
have been discussed so far, that are sublattice pseudospin [1], electronic real spin [2], andvalley-spin [3]. The fields concerning these DOFs are known as pseudospintronics, spintronics
and valleytronics, respectively. 2D materials possess both high carrier mobilities and DOFs,
which enables them to be a premium choice for the semiconductor industry [4].
Optical properties of the 2D materials have been studied extensively because the energy
bandgap covers a wide range of frequencies of electromagnetic wave, from far infrared toultraviolet [5–9]. The combination of electrical and optical properties offers possibilities forcontrolling electronic current or optical transitions characterized by different DOFs, which
results in huge potential in fundamental physics and the applications in electronic–photonic
devices.
In the monolayer transition metal dichalcogenides, thanks to the broken inversion symmetry
and strong spin-orbit coupling (SOC) [6], the polarization of the three DOFs [7, 10] is
observed experimentally. However, the three DOFs cannot be independent of one another forany existing materials or theoretical models, which disable independent usage of the spins.
Therefore, in order to obtain the complete independence of the DOFs, a special material thatoffers independent control of each DOF is needed for exploring physics and material science.
Here we propose a general Hamiltonian based on the Haldane model with SOC which
realizes the independence of all the DOFs that can tune optical absorption spectra as a functionof the SOC [11]. The present result suggests a new 2D material or a new 2D electronic device
which offers any combinations of pseudospintronics, spintronics and valleytronics applications
by means of circularly polarized light.
[1] K.-i. Sasaki, R. Saito, Prog. Theor. Phys. Suppl. 176, 253 (2008).
[2] M.N. Baibich, J.M. Broto, A. Fert, F. Nguyen Van Dau, F. Petroff, P. Etienne, G. Creuzet, A. Friederich, J.
Chazelas, Phys. Rev. Lett. 61, 2472 (1988).
[3] A. Rycerz, J. Tworzydlo, C.W.J. Beenakker, Nat. Phys. 3, 172 (2007).
[4] K.S. Novoselov, D. Jiang, F. Schedin, T.J. Booth, V.V. Khotkevich, S.V. Morozov, A.K. Geim, Proc. Natl.
Acad. Sci. U.S.A. 102, 10451 (2005).
[5] M. Ezawa, Phys. Rev. B 86, 161407(R) (2012).
[6] D. Xiao, G.-B. Liu, W. Feng, X. Xu, W. Yao, Phys. Rev. Lett. 108, 196802 (2012).
[7] K.F. Mak, K. He, J. Shan, T.F. Heinz, Nat. Nanotechnol. 7, 494 (2012).
[8] F. Bechstedt, L. Matthes, P. Gori, O. Pulci, Appl. Phys. Lett. 100, 261906 (2012).
[9] A. Zunger, A. Katzir, A. Halperin, Phys. Rev. B 13, 5560 (1976).
[10] H. Yuan, X. Wang, B. Lian, H. Zhang, X. Fang, B. Shen, G. Xu, Y. Xu, S.-C. Zhang, H.Y. Hwang, Y. Cui, Nat.
Nanotechnol. 9, 851 (2014).
[11] S. Wang, F. R. Pratama, M. S. Ukhtary, R. Saito, under review.
Corresponding Author: S. Wang
Tel: +81-22-795-7754, Fax: +81-22-795-6447,
E-mail: sake@flex.phys.tohoku.ac.jp- 42 -

3-9
Optical Properties of Monolayer Transition
Metal Dichalcogenides on GaN Surface Depending on their Polarity
S. Mouri1, Y. Komichi1, K. Shinokita2, K. Matsuda2 and T. Araki1
1

Ritsumeikan University, Nojihigashi 1-1-1, Kusatsu, Shiga, Japan,525-8577
Institute of Advanced Energy, Kyoto University, Gokanosho, Uji, Japan 611-0011

2

Optical properties of monolayer (1L) transition metal dichalcogenides (TMDs) show attractive
properties such as strong light-matter interactions [1], stable excitonic features [2-4] and valley-spin
polarization [5]. Therefore, they have enough potential as future novel optoelectronic devices.
Understanding of charge injection or extraction effect is indispensable towards the control of these
optical properties. One of the pathways to control the optical properties is to use the interaction 1LTMDs and supported substrate. GaN is known as the polar semiconductor whose surface state is strongly
modulated depending on its polarity. Here, we demonstrate the photoluminescence (PL) properties of
1L-TMDs due to the charge doping and/or charge transfer induced by GaN substrate.
The 1L-TMDs (MoS2, WSe2, and MoSe2) were transferred on the free standing GaN (Chino NitridesCo.) with Ga polar (+c) or N polar (-c) surface, and onto the standard SiO2/Si substrates as a reference.
Fig.1 shows the PL spectra of 1L-MoS2 supported on each substrate measured at room temperature. The
PL intensity of 1L-MoS2 on GaN substrates becomes weak around quarter as compared with that on
SiO2/Si, as shown in Figs. 1. These results suggest that the photocarrier transfer between MoS2 and GaN
surface at room temperature.
On the other hand, the spectral shape was changed depending on the polarity of supported GaN
substrate (+c, or –c). The exciton PL (X) of MoS2 was almost disappeared on N polar (-c) GaN, while
the trion (T) PL was slightly increased. The increase of trion spectral weight on N polar (-c) GaN
suggests the increase of doped-carrier density interacting with the excitons, which can be explained by
the electron accumulation at the interface of MoS2 and N polar (-c) GaN. From the band alignment in
MoS2/GaN interface, the downward band bending of N polar GaN [6] could causes the surface
accumulation of photo-induced electrons, which is
responsible to increase the trion population. The PL
quenching and increase of trion spectral weight in MoS2
were also observed in other TMDs (WSe2 and MoSe2) on
the GaN. These results strongly suggest that theengineering of polarity of supported substrate is one ofimportant pathways towards the optical device
applications of 1L-TMDs.
References[1] L. Britnell et al., Science 340, 1311 (2013).
[2] K. Fai. Mak et.al., Phys. Rev. Lett 105, 136805 (2010).
[3] A. Chernikov et.al., Phys. Rev. Lett 113, 076802 (2014).
[4] S. Mouri et.al., Phys. Rev. B 90, 155463 (2014).
[5] K. Fai. Mak et.al., Nat. Nanotech. 7, 494 (2012).
[6] M. Tangi et.al., Appl. Phys. Lett. 109, 032104 (2016).
Corresponding Author: S. Mouri
Tel:+81-77-561-2884
E-mail; iguchan@fc.ritsumei.ac.jp

Fig. 1．PL spectra of 1L-MoS2 on different
substrates, SiO2/Si, GaN (+c face), GaN (-cface) measured at room temperature.

- 43 -

3-10
Anomalous polarized Raman spectra of TaP○Riichiro Saito, Pang Xiaoqi, Wang Tong, Nguyen T. Hung1

Department of physics, Tohoku University, Sendai 980-8578, Japan

Polarized Raman spectra of TaP Weyl semimetal is discussed by analyzing resonant Raman
calculation. TaP is one of topological Weyl semimetals which attract much attention ofresearchers as an emerging material for discussing new physics such as the chiral Weyl fermion.
Recently Kunyan Zhang et al. observed the polarized Raman spectra of a single crystal of TaP
and they found that the polarized Raman spectra show anomalous patterns as a function of thepolarization direction of light that depends on laser excitation energy [1] ．In the normal
polarized Raman spectroscopy, the polarized Raman has a fixed shape for a given symmetry of
the Raman active mode, which does not change by changing the laser energy [2]. Thus thepresent results are exceptional in the theory of Raman spectroscopy.
In order to understand the anomalous behavior, we calculated the polarized Raman intensity
by the home-made program of resonant Raman intensity with using the calculated data of the
Quantum Espresso [3]. The calculate results reproduce the laser energy dependent polarized
Raman spectra. In order to understand the anomalous behavior of the polarized Raman spectra,
we restrict the Raman sub-processes intentionally in the resonant Raman calculation which
gives the conventional polarized Raman spectra. From this analysis we found that the origin of
the anomalous polarized Raman spectra comes from the quantum interference effect on Ramanprocesses for nearly degenerate conduction bands. In particular, for a specific laser energy, someRaman intensity vanished by the interference effect. In the presentation, we will show theanalysis based on the calculated results, which are compared with the experimental results.
This work is supported JSPS KAKENHI No. JPB18H01810.
References:[1] Kunyan Zhang et al., Phys. Rev. B, in press (2020). Related papers therein.
[2] R. Saito, Y. Tatsumi, S. Huang, X. Ling, M. S. Dresselhaus, J. of Phys: Cond. Matt., 28, 353002, (2016)[3] Y. Tatsumi, R. Saito, Phys. Rev. B 97, 115407 (2018).
Corresponding Author: Riichiro Saito
Tel: +81-22-795-7754, Fax: +81-22-795-6447,
Web: http://flex.phys.tohoku.ac.jp/
E-mail: rsaito@flex.phys.tohoku.ac.jp- 44 -

ポスター発表
Poster Preview

1 P – 1 ～ 1 P – 31
2 P – 1 ～ 2 P – 30
3 P – 1 ～ 3 P – 31

1P-1
Organic field effect transistor of fullerene C70 single crystals with rod shape○Ryohei Yamamoto1, Tadahiko Hirai 2, Nobuyuki Aoki 3 and Masaru Tachibana 1
1 Department of Materials System Science, Yokohama City University, Kanagawa 236-0004,

Japan

2 Commonwealth Scientific and Industrial Research Organisation

3 Graduate School of Advanced Integration Science, Chiba University, Chiba 263-8522

Organic semiconductors have received attention from both technological and academic
standpoints [1]. So the electrical properties of organic semiconductor are actively studied byusing field effect transistor. In p-type organic field effect transistors (OFETs) with single
crystals such as rubrene and tetacene, many studies showing high mobility have been reported[2] [3]. On the other hand n-type OFETs have been limited such as fullerenes [4] [5] and F16CuPc[6].
It is hoped that the mobility of the fullerene C 70 is higher than that of C60 due to the structureand electronic state [7]. However, researches on C70 FETs
were limited in thin films [8] because of difficulty of thegrowing single crystals. To understand the mechanism ofelectrical properties, it is important to use a single crystal.
Recently, we succeeded in the growth of C70 single
crystals by the liquid-liquid interface precipitation (LLIP)
method. In this study, we report the results of structure andelectrical measurements of C70 single crystals FETs.
The C70 crystals were grown by the LLIP method withusing m-xylene and 2-propanol as good and poor solvents.
The C70 crystals ware evaluated by an optical microscope,
Scanning electron microscope
scanning electron microscope (Fig.1), Fourier-transform Fig.1
image of C70 crystals
infrared spectroscopy and powder X-ray structural
analysis.
Output characteristics of C70 single crystals FETs exhibits typical feature of n-type of OFETs.
It is known that water and oxygen are easily adsorbed into C 70 crystals in air and degrade
mobility of C70 crystals. To remove water and oxygen, the FET devices were annealed at 374
K under vacuum condition. The carrier mobility was significantly increased by the annealing
treatment, and value was 1.22×10-2 cm2/Vs.
[1] R. W. I. de Boer, M. E. Gershenson, A. F. Morpurgo, and V. Podzorov, phys. Stat. sol., 201, 1302 (2004).
[2] A. L. Briseno, et al., Nature, 444, 913 (2006).
[3] S. Terao, et al., J. Appl. Phys., 108, 124511 (2010).
[4] K. Ogawa, et al., Appl. Phys. Lett. 88, 112109 (2006).
[5] H. Li, et al., J. Am Chem. Soc. 134, 2760-5 (2012).
[6] H. Jiang, et al., J. Mater. Chem., 21, 4771 (2011).
[7] S. Saito and A. Oshiyama, phys. Rev B 44, 11532 (1991).
[8] S. Zheng and X. Lu, RSC Adv., 5, 38202 (2015).

- 45 -

1P-2







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­  ­­¡

- 46 -

1P-3
Mechanical properties and morphology of polypropylene/
ethylene-1-butene copolymer rubber/CNT composites○Yoshimi Muraoka, Kenzo Fukumori*Toyota Central Research and Development Laboratories, Inc, Nagakute 480-1192, Japan
CNT (carbon nanotube) is one of the most promising materials as a reinforcing nanofiller forpolymers since it has excellent characteristics such as high stiffness, strength, toughness andso on. Many researches have been carried out to improve mechanical properties by adding
small amount of CNT to polymers[1]. Although the mechanical properties of polymer/CNT
composites were improved by loading CNT, it is still unclear in detail about the effects of theincorporation of CNTs on the mechanical properties.
In this study, we have investigated the relation between flexural properties and morphologies
of polypropylene (PP) based polymer blends/CNT composites, dependent on the kind of CNT,
for automobile applications. The composites were prepared by melt blending of PP,
ethylene-1-butene copolymer rubber (EBR) and CNTs with a twin-screw extruder. Fig. 1
shows the flexural moduli of the composites depending on the CNT amount. In the case ofusing CNT60 (diameter:60nm, G/D ratio:ca.8.0), the flexural modulus of CNT60 composite
was superior to that of CNT15 (diameter:5nm, G/D ratio:ca.1.0) composite. The morphologiesof those composites shown in Fig. 2 were observed by scanning electron microscopy (SEM).
Depending on the kind of CNT, the morphology of the CNT60 composite was quite different
from that of the CNT15 composite. That is, in the CNT60 composite, CNTs partially wrappedby the EBR domains were dispersed in PP matrix. On the other hand, in the CNT15 composite,
CNTs were selectively localized in the EBR domains. Thus, it is confirmed that themorphology of the CNT composites, dependent on the kind of CNT related with diameter and
G/D ratio, plays a key role in enhanced mechanical properties.
CNT60

PP

EBR

CNT

2μm
PP

CNT15

EBR
2μm
Fig.1 The relationship between CNT content andflexural modulus

CNT

Fig.2 SEM images of composite materials andtheir schematic illustrations[1] M. Khodabandelou , et al. Polym. Bull. 73, 1607 (2016).
Corresponding Author: Y. Muraoka
E-mail: e4782@mosk.tytlabs.co.jp*Present address: Aichi Institute of Technology.

- 47 -

1P-4
Understanding the Effect of Sulfur on the Synthesis of Carbon Nanotubes○ Rei NAKAGAWA1, Michiko EDO1, Hisashi SUGIME1, Suguru NODA1,2,*
1
Department of Applied Chemistry, 2Waseda Research Institute for Science and Engineering,
Waseda University, Tokyo, Japan
Carbon Nanotubes (CNTs) are attractive with high hopes in many different fields fortheir excellent properties. However, the practical applications of CNTs has been a challenge
due to their high price and/or insufficient quality. Floating catalyst chemical vapor deposition(CVD) enables the synthesis of high quality CNTs, but it has had an issue with its low catalyst
usage. To combat this situation, many groups have conducted research to improve theproductivity of this process, and as a result it has been reported that the implementation of sulfur
can increase the overall yield of floating catalyst CVD [1]. Many groups have proposed positiveroles of sulfur; Fe-S to be the active site for catalytic reaction or reduced surface energy of FeS for nucleation of small Fe particles. However, these models are not supported by clear
evidences and are not applicable to supported catalysts.
Here, we propose an opposite model where sulfur deactivates the Fe catalyst. Small
amount of sulfur forms an inactive region on a Fe particle, and the inactive region works as an
entrance for the carbon source without being
covered with graphitic carbon. The analysis of
this is difficult for floating catalysts, therefore
for this research, supported catalysts were usedby implementing graphite sheets as substrates
to replicate the floating catalysts with sphericalstructure. Scanning electron microscope(SEM) shows that CNTs were only synthesizedwhen S was supplied during synthesis (Fig.

a.) Effect of Sulfur
S (g)FeGraphite sheet

w/o S

Fe
Graphite sheet

Al2O3 : 0.25, 0.5, 1.0 nm

w/o Al2O3

500 nm

500 nmw/ S1a). Additionally, to confirm the importance of
having an inactive region within the catalyst
particle for CNT synthesis, a thin Al2O3 layer
was deposited on top of the Fe catalysts. The
thin Al2O3 layer significantly enhanced theCNT growth (Fig. 1b) in a similar manner assulfur. These results suggests a new approachfor future catalyst design.

b.) Effect of Al2O3

w/ Al2O3

500 nm

500 nm
Fig. 1. SEM analysis of graphite substrates after
CNT synthesis. (a) Sulfur vapor was supplied to the
Fe catalyst during synthesis. (b) Al2O3 thin layer
was deposited on the Fe catalyst.

[1] H.M. Cheng, et al., Appl. Phys. Lett. 72, 3282 (1998).
Corresponding Author: S. Noda, Tel&Fax: +81-3-5286-2769, E-mail: noda@waseda.jp- 48 -

1P-5
Evaluation of various nitrogen-doping in graphene on the performance as asupercapacitor electrode○Rohit Yadav, Prerna Joshi, Masanori Hara, Masamichi Yoshimura
Graduate School of Engineering, Toyota Technological Institute, Nagoya 468-8511, Japan
A supercapacitor is an energy storage device with high charge storage capacity and excellent
cyclic stability due to its large surface area and easy ion accessibility. It is categorized into
electric double-layer capacitors (EDLCs), pseudocapacitors and hybrid capacitors, on the basisof their charge storage mechanism. EDLC behaviour is commonly shown by carbon-basedmaterials, where charge storage takes place via electrolyte ion intercalation inside porous
electrode material forming an electrostatic double layer, resulting in the charging of EDLC. On
the other hand, charge storage in pseudocapacitors takes place via oxidation and reduction(redox reaction) of the electrode with electrolyte ions. Among available carbon materials for
EDLC, graphene emerged as a potential candidate due to its high mechanical strength (Young’s
modulus of ~490 kPa)[1], large surface area (~2630 m2/g)[2], and high electrical conductivity(~5 10-3 S/cm)[3]. However, in the case of pristine graphene, the stacking of sheets via vander Waals interaction decreases the surface area, resulting in low intrinsic capacitance [4]. To
overcome this limitation, we have incorporated nitrogen (N) into the reduced graphene oxide(N-rGO) lattice via pyrolysis in the presence of urea at various temperatures (600, 700, 800,
900 oC) in inert atmosphere. Synthesized N-rGO samples were characterized using both
physical and electrochemical techniques.
X-ray photoelectron spectroscopy (XPS) and Energy-dispersive X-ray (EDX) spectroscopy
showed uniform and varying nitrogen doping from 15 to 5.8 at. %, with an increase in pyrolysis
temperature from 600 oC to 900 oC. N-rGO synthesized at 800 oC showed the highest specificsurface area and thus the highest areal capacitance of 138.4 mF/cm2 from the charge-discharge(CDC) profile. The capacitance shows an exceptional increment of 21.7% after 10000 cycles
of charge-discharge, as shown in fig.1.
The increased capacitance after stability
could be due to the electrochemical
activation of nitrogen functionality or
oxygen functional group at the surface ofthe electrode upon continuous cycling, asconfirmed by cyclic voltammetry (CV)after stability. The above characterizations
reveal the potential use of N-rGO as anactive material for supercapacitor
electrode.
[1] H. H. Huang et al. Sci. Rep. 8, 6849 (2018).
[2] M. D. Stoller et al. Nano Lett. 8, 3498 (2008).
[3] Y. Xu et al. ACS Nano 4, 4324 (2010).
[4] L. Sun et al. RSC Adv. 2, 4498 (2012).
Corresponding Author: Masamichi Yoshimura
Tel: +81-52-809-1851
E-mail: yoshi@toyota-ti.ac.jp

Fig. 1. Cyclic stability of N-rGO at 800 °C andinset: CV before and after stability.

- 49 -

1P-6
Gene expression analysis of macrophages on carbon nanohorn coatedtitanium○Sadahito Kimura1, Eri Hirata1＊, Sari Takada1, Masatoshi Sakairi2, Masako Yudasaka3,
Atsuro Yokoyama1
1

Graduate School of Dental Medicine, Hokkaido University, Kita 13, Nishi 7, Kita-ku,
Sapporo 060-8586, Japan.
2
Division of Materials Science and Engineering, Faculty of Engineering, Hokkaido
University, Kita 13, Nishi 8, Kita-ku, Sapporo 060-8628, Japan.
3
Nanomaterials Research Institute (NMRI), National Institute of Advanced Industrial
Science and Technology (AIST), Tsukuba Central 5, 1-1-1 Higashi, Tsukuba 305-8565 Japan.
Carbon nanohorns (CNHs) are expected to be applied to biomaterials due to their physicaland biological properties. Previously, we have concentrated on CNHs and osteogenesis anddocumented enhancing osteogenesis under the CNH membrane[1] and promoting osteoblast
differentiation by macrophages engulfing CNHs[2]. In this study, titanium was coated with
CNHs due to apply for dental implants, and inflammatory cytokines and gene expression ofmacrophages cultured on them were analyzed.
CNHs were electrodeposited on the Ti surface (CNH / Ti). Mouse-derived monocyte
macrophage-like cells (J774A-1) were cultured on CNH / Ti. SEM and TEM observations werecarried out after 24 and 72 hours. The cytokines (TNFα, IL-6, IL-10) in the culture supernatantwere measured by ELISA. Microarray analysis was performed using the RNA of the cells
cultured for 24 hours.
By TEM observation, some CNHs was observed in the cells. The amounts of TNFα and IL6 on CNH / Ti were significantly lower than those on Ti, and there was no significant differencein IL-10. TNFα and IL-6 are known as inflammatory cytokines secreted by M1-type
macrophages to be inhibitors of bone formation. IL-10 is known as an anti-inflammatory
cytokine by M2 macrophages.
Gene Ontology analysis by microarray showed genes related to transcription, repair andreplication of macrophage DNA in CNH / Ti were down-regulated compared to Ti.
Therefore, CNHs on the Ti surface might regulate transcription, repair and replication of
DNA of macrophage, and effect on production of inflammatory cytokines.
[1] Kasai T, Yudasaka M,Yokoyama A,et al.: Carbon nanohorns accelerate bone regeneration in rat calvarial bone
defect. Nanotechnology,2011,22,065102-065110[2] Hirata, E,Yudasaka M,Yokoyama A,et al.: Carbon nanohorns allow acceleration of osteoblast differentiation
via macrophage activation. Nanoscale, 2016, 8, 14514-145
Corresponding Author: E.Hirata
Tel: +81-011-706-4270, Fax: +81-011-706-4903,
E-mail: erieri@den.hokudai.ac.jp- 50 -

1P-7
Unidirectional bright exciton transport in a WS2xSe(2-2x) alloy monolayer○Masafumi Shimasaki1, Taishi Nishihara1, Naoki Wada2, Zheng Liu3, Kana Kojima2,
Keisuke Shinokita1, Kazunari Matsuda1, Yasumitsu Miyata2, Yuhei Miyauchi1
1

Institute of Advanced Energy, Kyoto University, Uji, Kyoto 611-0011, Japan
Department of Physics, Tokyo Metropolitan University, Hachioji, Tokyo 192-0397, Japan
3
Inorganic Functional Materials Research Institute, AIST, Nagoya, Aichi 463-8560, Japan
2

Recently, spatial motion of two dimensional (2D) excitons in monolayer transition metal
dichalcogenides (TMDCs) has attracted growing interest because 2D exciton motion plays
essential roles in intriguing phenomena such as exciton valley Hall effect [1] and Halo-shaped
luminescence pattern [2]. Additionally, tunable exciton transport, which is essential for
exciton transistors, has been demonstrated via exciton energy modulation by applying
out-of-plane electric field on interlayer excitons in vertical heterostructure MoS 2/WSe2 [3].
These studies clearly indicate that development of the manipulation method of the 2D exciton
motion offers new opportunities for both exploring fundamental physics and developing novel
optoelectronic devices relying on the 2D exciton motion and interconversion of excitons andphotons. However, controlling transport of intralayer bright excitons in monolayer TMDCs,
which is expected to show the strongest coupling with photons among various excitonic
species in TMDCs, still remains a challenge because they are hardly driven by the electricfield owing to their strongly bound nature and inherent in-plane dipole.
Here, we demonstrate unidirectional transport of bright excitons in WS2xSe(2-2x) alloy
monolayer driven by exciton energy gradient due to gradual alloy composition change in one
direction. The built-in exciton energy gradient was generated using tunable exciton energy in
TMDC alloys [4] depending on the composition ratio. WS2xSe(2-2x) alloy monolayers weregrown on SiO2/Si substrate using salt-assisted chemical vapor deposition method [5]. We
confirmed the emergence of the unidirectional exciton energy gradient (0-22 meV/m) over
20 µm using spatially resolved photoluminescence (PL) mapping, and then measured PL
images to examine the exciton transport on the gradient. An abrupt displacement of theexciton PL spot from the excitation spot was observed at the regions with the large energy
gradient, in contrast to the coincidence of the excitation and PL spots at nearly pure WS2 andWSe2 regions with negligible exciton energy gradient. The displacements depending on theenergy gradient could be well reproduced in numerical simulations using a drift-diffusion
equation; this confirms that the observed phenomena originate from non-diffusive exciton
transport driven by the gradient induced force. These findings may offer new opportunities tostudy exciton transport related physics and facilitate development of the 2D excitonic devices.
[1] M. Onga et al. Nat. Mater. 16, 1193 (2017).
[2] M. Kulig et al. Phys. Rev. Lett. 120, 207401 (2018).
[3] D. Unuchek et al. Nature 560, 340 (2018).
[4] X. Duan et al. Nano Lett. 16, 264 (2016).
[5] H. E. Lim et al. Nanoscale 11, 19700 (2019).
Corresponding Author: Y. Miyauchi
Tel: +81-774-38-3463
E-mail: miyauchi@iae.kyoto-u.ac.jp- 51 -

1P-8
Electronic structures of bundles of molybdenum disulfide nanotubes○Kaoru Hisama1, Mina Maruyama2, Susumu Okada2, Shohei Chiashi1and Shigeo Maruyama1,3
1

Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan2

3

Department of Physics, University of Tsukuba, Tsukuba 305-8571, Japan

Energy NanoEngineering Lab., National Institute of Advanced Industrial Science and Technology(AIST), Ibaraki 305-8564, Japan

nm

Energy [eV]0.3

Energy [eV]Transition metal dichalcogenides (TMDs) can form a tubular form, owing to their
two-dimensional networks with three-atom thickness. By analogy with carbon nanotubes,
TMD nanotubes are expected to exhibit unusual electronic properties that are absent in theirplanar form. Several theoretical works reported that the electronic structures of their tubular
forms depend on their chirality [1,2]. As well as the chirality, interaction with other TMD
walls in bundles must cause an electronic structure modulation, because the electronic
structure of planar TMD strongly depends on the interlayer interaction. However, reports on
the influence of the interwall interaction in bundled and multi-walled TMD nanotubes on theirelectronic structure are absent to date. Therefore, we investigate the electronic structures ofbundles of molybdenum disulfide nanotubes (MoS2 NTs) using the density functional theory.
Here, we consider a bundle of (15,0) MoS2 NTs each of which is separated by 0.3 nm
vacuum spacing with its six adjacent NTs [Fig. 1(a)]. Figure 1(b) shows the calculated band
structure of the bundle of (15,0) MoS2 NTs along the high symmetry points. Along the tube
direction corresponding to the G-A line, the dispersion relation of the bundle retains that of an
isolated NT shown in Fig. 1(c). This implies that the intertube interaction is negligible.
However, it is not the case if carefully checked the dispersion relation along normal direction
to the NT: The highest occupied states possessed substantial band dispersion of 0.3 eV,
indicating that the intertube wave hybridization is important to determine the low energy
electronic properties of the bundles. Indeed, the bundle is not the direct band gap
semiconductor but indirect band gap semiconductor where the valence band and the
conduction band edges are located at the K and Γ points, respectively.
(b)
(a)
(c)

Figure 1 (a) Geometric structure of a bundle of (15,0) MoS2 NTs with the interwall spacing of 0.3nm
and electronic structures of (b) the bundle of (15,0) MoS2 NTs and of (c) an isolated (15,0) MoS2 NT.
[1] G. Seifert, et al., Phys. Rev. Lett. 85, 146 (2000).[2] D. –B. Zhang, et al., Phys. Rev. Lett. 104, 065502 (2010).
Corresponding Author: Shigeo Maruyama

E-mail: maruyama@photon.t.u-tokyo.ac.jp- 52 -

1P-9
Rayleigh scattering measurement of suspended SWCNTs
coaxially wrapped with BNNTs○Satoshi Yotsumoto1, Hayato Arai1, Yongjia Zheng1, Taiki Inoue1, Rong Xiang1,
Shigeo Maruyama1, 2, Shohei Chiashi1
12Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan
Energy NanoEngineering Laboratory, National Institute of Advanced Industrial Science andTechnology (AIST), Ibaraki, 305-8564, Japan
Single-walled carbon nanotubes (SWCNTs) are one of the most promising materials for

optoelectronics devices because of their unique properties, and it is known that theirsurrounding environment influences their physical properties. Rayleigh scattering spectroscopy[1] is a powerful method to analyze the optical properties of SWCNTs. Recently, onedimensional van der Waals heteronanotubes which consist of SWCNTs and boron nitride
nanotubes (BNNTs) are reported [2] and the BNNT is expected to work as the protect layer
because of its high chemical stability. However, the influence of BNNT on the property of
SWCNT is not revealed.
In this study, SWCNT-BNNT heteronanotubes were synthesized, and their Rayleigh spectra
were investigated. The supercontinuum laser (the range of wavelength is 450 – 2400 nm) wasused as the excitation light. Suspended SWCNTs were synthesized by fast-heating chemical
vapor deposition (CVD) [3] across open slit structures (width 20 – 40 μm) fabricated on SiO2/Si

Intensity (a.u.)

substrates. We used a thin film (~0.2 nm) of Fe as the catalyst and ethanol as the carbon source
for CVD growth at 900 ℃. After measuring Rayleigh scattering from pristine SWCNTs,
BNNTs were synthesized by CVD using ammonia borane (NH3BH3) as the BNNT precursor.
After BNNT growth, it was found that the optical transition energy of SWCNTs was red-shifted(Fig. 1) as a result of both increasing of
the dielectric screening due to BNNTSWCNT@BNNT
coating and decreasing of it due todesorption of water molecules.
[1] M. Y. Sfeir et al., Science 306, 1540 (2004).
[2] R. Xiang et al., Science, in press, doi:

S33

pristine SWCNT
S55

10.1126/science.aaz2570.
[3] S. Huang et al., Nano Lett. 4, 1025 (2004).

1.6

Corresponding Author: S. Chiashi
Tel: +81-3-5841-6408, Fax: +81-3-5841-6408,
E-mail: chiashi@photon.t.u-tokyo.ac.jp

S44

2
2.4
Energy (eV)2.8

Fig. 1 Rayleigh spectra of a (28,5) SWCNT before andafter BNNT growth.

- 53 -

1P-10
Optical properties of inorganic nanotubes with different diameters○Yohei Yomogida, Yasumitsu Miyata, and Kazuhiro Yanagi
Department of Physics, Tokyo Metropolitan University, Tokyo 192-0397, Japan

Absorbance peak energy (eV)AbsorbanceAbsorbanceInorganic nanotubes have a cylindrical structure of transition-metal dichalcogenide sheets
and advantages for semiconductor applications because of their semiconducting properties
regardless of how they are rolled. Moreover, recent studies have revealed potential applicationsin optoelectronics, such as high-performance photovoltaic effect [1]. Such application
performance is affected by the band structure and optical properties, which is strongly
dependent on their nanotube structure. Thus, it is important to understand structure-dependent
optical properties. However, systematic experiment has not been investigated. Here, we
prepared inorganic nanotubes with different diameters and clarified relationship between theirdiameters and optical properties.
Inorganic nanotubes with different diameters
Upper peak Lower peakwere prepared by two approaches: structure sorting
through centrifugation [2] and synthesis via
sulfurization of solution-synthesized oxide
Structure-sorted
nanowires [3]. For structure sorting, inorganic
WS -NTscentrifugation
2
nanotubes with various diameters (~100 nm inUpper peakmean diameter) was used as an original sample andLower peaksorted them by density. On the other hand, thesynthesis can produce relatively small-diameter
Synthesized WS -NTs
WS2 nanotubes (20 nm in mean dimeter).
2
Fig. 1 shows absorption spectra of the sample
300 400 500 600 700 800
with different diameters. The obtained WS2
Wavelength (nm)nanotubes show optical transition peaks, including
Fig. 1 Absorption spectra of WS2
lower A-exciton peaks around 600-7
nanotubes with different diameters
00 nm and upper B-exciton peaks around 500600 nm. These peaks have strong correlation with
3
EC
diameter of the sample. The structure-sorted largediameter sample shows longer wavelength
absorption, while the synthesized small-diameter
2.5
EB
Upper peaksample shows the shortest wavelength absorption.
Fig. 2 shows the relationship between the diameterand absorbance peak energy. We found the
EA
Lower peak2
absorption peak energy of A- (EA) and B-exciton(EB) was red-shifted with an increase in the
diameter. This behavior can be understood byconsidering a strong coupling between the exciton
1.5
20 40 60 80 100 120 140
and photon that is confined in cavity of inorganic
Mean diameter (nm)nanotubes.
Fig. 2 Relationship between
diameterand absorption peak energy.
[1] Y. J. Zhang et al, Nature 570, 350 (2019)[2] Y. Yomogida et al, ACS Omega 9, 075001 (2018)[3] Y. Yomogida et al, Appl. Phys. Express 12, 085001 (2019)- 54 -

1P-11

Chemical vapor deposition of one-dimensional heterostructures○Yongjia Zheng1, Yang Qian1, Ming Liu1, Akihito Kumamoto1, Yuichi Ikuhara1, Anton Anisimov2,
Esko I. Kauppinen3, Shohei Chiashi1, Taiki Inoue1, Rong Xiang1, Shigeo Maruyama1,4
Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan
2
Canatu Ltd., Konalankuja 5, FI-00390 Helsinki, Finland3
Department of Applied Physics, Aalto University, Otakaari 1, 02150 Espoo, FI-20742, Finland
4
Energy NanoEngineering Lab., National Institute of Advanced Industrial Science andTechnology (AIST), Tsukuba. 305-8564, Japan1

In recent years researchers have focused on two-dimensional van der Waals (vdW)
heterostructures, which have generated great interests recently due to the possibility of combining
diverse atomic layers to create novel materials and devices [1-2]. In this work, we demonstrate a
new one-dimensional structure with similar heterostructure interfaces that combines the singlewalled carbon nanotubes (SWCNTs), boron nitride nanotubes (BNNTs) and Molybdenum Disulfide(MoS2) nanotubes in the radial direction. Techniques involving direct growth of 1D vdWH bychemical vapor deposition (CVD) will be presented in detail. Ammonia borane (BH3NH3) as
precursor was directly used to synthesize BNNTs with the aid of SWCNTs as a template by a facile
CVD technique. MSNTs are synthesized on as-prepared SWCNTs/BNNTs by CVD using MoO3
and S powders as the reactants. In Fig. 1a-d, STEM images and EELS mapping clearly show aternary nanotube that consists of SWCNT-BNNTs-MSNTs in a coaxial structure [3]. What’s more,different kinds of one-dimensional structures, such as SWCNT-BNNTs-CNTs, are also achievableusing our CVD method, as shown in Fig. 1e-f. We believe these one-dimensional structures will
have a broad interest and impact in many fields, which include but not limited in investigating the
intrinsic optical properties of environment-isolated SWCNTs, fabricating BN-protected or gated
SWCNT devices and building more sophisticated 1D material systems. It can also be used forphotovoltaics and light-emitting devices when combining different kinds of transition metal
dichalcogenide monolayers (TMDC) materials.

Fig. 1: (a) Atomic model, (b) HAADF-STEM image, (c) annular bright field (ABF)–STEM imageand (d) EELS mapping of a 5 nm diameter ternary nanotubes consisting one layer of carbon, threelayers of BN and one layer MoS2 nanotube. Scale bar, 5 nm. (e) Atomic model and (f) TEM imageof a ternary nanotubes with an inner SWCNT and outer layers of BN and carbon. (g) Atomic modeland (h) TEM image of a multi-walled CNT grown from a SWCNT.
[1] D. Jariwala et al., Nature materials, 16, 170 (2017).
[2] Z. Liu et al., Nature Nanotechnology, 8, 119 (2013).
[3] R. Xiang et al., Science, accepted (2020).

- 55 -

Corresponding Author: S. Maruyama
Tel: +81-3-5841-6421,
Fax: +81-3-5841-6983,
E-mail: maruyama@photon.t.u -tokyo.ac.jp

1P-12Synthesis and Raman scattering spectroscopy of gas-flow oriented
single-walled carbon nanotubes on hexagonal boron-nitride○Shu Sato1, Satoshi Yotsumoto1, Masanori Bamba1, Taiki Inoue1, Shigeo Maruyama1,2,
Shohei Chiashi1
1Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan.
Energy Nano Engineering Laboratory, National Institute of Advanced Industrial Science andTechnology (AIST), Tsukuba 305-8564, Japan.

2

It is known that the properties of single-walled carbon nanotubes (SWCNTs) are
affected by the environmental conditions around them. For example, the semiconducting
SWCNTs that are suspended [1] or dispersed in solution [2] emit photoluminescence (PL),while those on silicon substrate do not. On the other hand, semiconducting SWCNTs on
hexagonal boron nitride (h-BN) show PL emission [3]. Recently, the synthesis of theheterostructure of SWCNTs and boron nitride nanotubes (BNNTs) [4] is reported. These
complex systems of SWCNT and h-BN are interesting, however, their properties areveiled. In this study, we directly synthesized SWCNTs on h-BN based on the gas-floworiented CVD method [5] and investigated the optical properties by using Raman
scattering spectroscopy.
SWCNTs were synthesized from Fe catalyst. SEM images in Fig. 1(a, b) show
the growth of gas-flow oriented SWCNTs with and without fast-heating process, which
is often used for gas-oriented growth. While the fast-heating process enhanced the numberof oriented SWCNTs, the enough long pre-reduction and CVD times were more important
for the gas-flow oriented growth. Using the gas-flow oriented growth technique,
SWCNTs were directly synthesized on exfoliated h-BN. The scanning Raman
measurement (Fig. 1(c)) shows that a SWCNT was clearly lying on the surface of h-BN
and that the G-band of the SWCNT on h-BN exhibited the downshift comparing to thaton SiO2 (Fig. 1(d)). The downshift was also observed from suspended SWCNT@BNNT
and it might come from the interlayer interaction between SWCNTs and BNNTs.
(b)

(d)

(c)

Gas flow
directionh-BN

100 μmSiO220μm

100 μmIntensity (arb. units)

(a)

1500

on h−BN1550

on SiO2

1600−1

Raman Shift (cm )1650

Figure 1 (a, b) SEM images of SWCNTs (a) with and (b) without using fast-heating process. (c) Scanning
Raman image of the G-band intensity from SWCNT on h-BN. (d) G-band of SWCNT on h-BN (whitecircle of Fig.1 (c)) and on SiO2 substrate (black circle of Fig.1 (c)).
[1] J. Lefebvre, et.al., Phys. Rev. Let., 90, 217401 (2003). [2] S. M. Bachilo, et.al., Science, 298, 2361
(2002). [3] J. C. Noé, et.al., Nano Lett. 18, 4136. (2018). [4] R. Xiang, et.al., Science, in press, doi:
10.1126/science.aaz2570. [5] S. M. Huang, et al., Nano Letters 4, 1025 (2004).
Tel/Fax: +81-3-5841-6408, E-mail: chiashi@photon.t.u-tokyo.ac.jp- 56 -

1P-13In-Plane Thermal Conductance of Thin Films Composed of CoaxiallyCombined Single-Walled Carbon Nanotubes and Boron Nitride Nanotubes○Pengyingkai Wang1, Yongjia Zheng1, Taiki Inoue1, Rong Xiang1, Ahmed Shawky 1,2
Makoto Watanabe1, Anton Anisimov 3, Esko I. Kauppinen 4, Shohei Chiashi1, Shigeo Maruyama1, 5

Department of Mechanical Engineering, the University of Tokyo, Tokyo 113-8656, Japan
Nanomaterials and Nanotechnology Department, Advanced Materials Division, Central
Metallurgical R&D Institute (CMRDI) P.O. Box 87 Helwan 11421, Cairo, Egypt
3
Canatu, Ltd., Konalankuja 5, FI‐00390 Helsinki, Finland4
Department of Applied Physics, Aalto University School of Science, 15100, FI-00076 Aalto, Finland
5
Energy Nanoengineering Lab, National Institute of Advanced Industrial Science and Technology(AIST), Ibaraki 305-8564, Japan
1

2

Carbon nanotubes (CNTs) and boron nitride nanotubes (BNNTs) are one-dimensional
materials with high thermal conductivity and similar crystal structures [1, 2]. Additionally,
BNNTs feature higher thermal and chemical stability in air than CNTs.
In this work, a single-walled carbon nanotube (SWCNT) film [3] was used as a template
to synthesize a BNNT coating by the chemical vapor deposition (CVD) method to form a
coaxial heterostructure [4]. Then, a contact-free steady-state infrared (IR) method was adopted
to measure the in-plane sheet thermal conductance of the as-synthesized film [5]. The
heterostructured SWCNT-BNNT film demonstrates an enhanced sheet thermal conductancecompared with the bare SWCNT film. The increase in sheet thermal conductance shows areverse relationship with SWCNT film transparency. An enhancement of over 80 % (from ~3.6
μW∙K-1∙sq-1 to ~6.4 μW∙K-1∙sq-1) is attained when the BNNT coating is applied to an SWCNT
film with a transparency of 87 % as shown in Figure 1 [6]. Theoretical study on thisheterostructure will be further discussed.

Figure 1. (a) Sheet thermal conductance of bare SWCNT films and annealed ones. (b) Comparison between
annealed SWCNT films and BNNT-SWCNT films together with the increase ratio. (c) Sheet electrical conductanceof bare, annealed, and BNNT-coated SWCNT films.
[1] J. Hone et al., Appl. Phys. Lett., 77, 666 (2000). [2] S. Kaur et al. Nat. Commun., 5, 3082 (2014).
[3] A.G. Nasibulin et al., ACS Nano, 4, 5(2011).
[4] R. Xiang et al., Science, in press, doi: 10.1126/science.aaz2570.
[5] Y. Feng et al., Jpn. J. Appl. Phys., 57, 075101 (2018). [6] P. Wang et al., submitted.
Corresponding Author: S. Maruyama, Tel: +81-3-5841-6421, Fax: +81-3-5800-6983,
E-mail: maruyama@photon.t.u-tokyo.ac.jp- 57 -

1P-14Fabrication of ribbon-like films with highly oriented carbon nanotubes
using a robotic dispenser○Manish Pandey, Ryo Abe, Naofumi Okamoto, Yuki Sekimoto, Masakazu Nakamura
Division of Materials Science, Nara Institute of Science and Technology,
8916-5 Takayama-cho, Ikoma, Nara 630-0192, Japan
Carbon Nanotubes (CNTs) possess tremendous
potential applications owing to their excellent
mechanical, electrical and thermal properties [1-2].
Although experimental and theoretical studies suggestthat isolated CNTs possess excellent anisotropic
physical properties; however, in general, bulk CNT
networks are highly random. Therefore, bulk
fabrication of aligned CNT films is expected to bereally important for many applications to getanisotropic and high thermal and electricalconductivity along the CNT orientation direction.
In this work, we will report a new method of
fabricating the ribbon-like CNT/polymer composite
films using a programmed robotic dispenser as Fig. 1 Schematic of the film preparation
illustrated in Fig. 1 This method can easily produce a using robot dispenser
controlled orientation of the CNTs along the length
direction of the ribbon. The orientation characteristics
along the length remain similar throughout the lengthof the film whereas width of these films and orientation
intensities are interrelated and depend on the CNT
composite and casting conditions which will bereported in detail. Orientation characteristics were
estimated by polarized Raman mapping. These
preliminary results reveal that CNTs are effectively
oriented with a high degree of orientation at the center
that gradually decreases towards the edges. The Fig. 2 Raman mapping results obtained byrepresentative mapping of the G-band intensity ratio is imaging the G-band intensity and taking
shown in Fig. 2. The areas of higher intensity represent
areas with highly aligned CNTs whereas areas of low their ratio with laser parallel andintensity represent areas of randomly oriented CNTs. perpendicular to the film drawing direction.
The thermal diffusivity of oriented films was found to be significantly higher in comparison
to randomly oriented CNT films and will be reported in detail.
This work was supported by JST CREST Grant Number JPMJCR18I3, Japan.
[1] Shokrieh et al. Mech Compos Mater 46, 155–172 (2010).
[2] Z. Han, Alberto Fina, Progress in Polymer Science 36, 914-944 (2011).
Corresponding Author: M. Nakamura
Tel: +81- 743-72-6031, Fax: +81-743-72-6047, E-mail: mnakamura@ms.naist.jp- 58 -

1P-15
Phosphorescence of polyynes: A key probe for the detection ofa new series of laser ablated polyyne derivatives○Tomonari Wakabayashi1, Nozomu Kitamura1, Ayato Osawa1, Daiki Okada1, Hal Suzuki1,
Yusuke Morisawa1, and Miho Hatanaka2
Department of Chemistry, Kindai University, Higashi-Osaka, Osaka 577-8502, Japan
Institute for Research Initiatives, Graduate School of Science and Technology, and Data
Science Center, Nara Institute of Science and Technology (NAIST), Ikoma 630-0192, Japan1

2

Laser ablation of particulate carbon in liquidorganic solvents is a promising technique for
production of macroscopic amounts of polyyne
molecules [1]. Along with the series of hydrogencapped polyynes, H(C≡C)nH (n = 4-9), some series ofpolyyne derivatives are formed as by products, e.g.,
methylpolyynes, H(C≡C)nCH3 (n = 5-7) [2], andcyanopolyynes, H(C≡C)nCN (n = 3-6) [3].
Phosphorescence spectroscopy is applied recently
to the study of electronic transitions of polyyne
derivatives embedded in cryogenic matrices [4]. We
demonstrate here that phosphorescence is a key probe
for the detection of a new series of polyyne
derivatives with conjugate linear sp-carbon chains.
We found recently a new series of polyyne
derivatives by characteristic UV absorption spectra
having a peak maximum at 206, 234, 260, or 284 nm[5]. For the molecular structure, resonance-enhanced
multiphoton-ionization (REMPI) mass spectroscopy,
resonance Raman spectroscopy, and phosphorescence
spectroscopy were examined. Fig. 1 shows a typicallaser induced phosphorescence spectrum of a polyyne
derivative, namely U234, isolated in a cryogenic
matrix host of solid hexane at 20 K [5]. The origin
band at 532 nm and the vibrational progression of~2150 cm-1 are clearly seen. Lifetime of ~30 msec
was derived from temporal decay of phosphorescenceintensity. Fig. 2 compares the origin bands of U234 at
234 nm and 532 nm with the observed transition
wavelengths for UV absorption and phosphorescenceof hydrogen-capped polyynes [6].

Fig. 1. Phosphorescence spectrum of a polyyne
derivative U234 in a cryogenic matrix host.

Fig. 2. Sp-carbon chain-length dependence ofthe electronic-transition wavelengths forhydrogen-capped polyyne molecules (opensymbols) and a new series of polyyne
derivatives (closed symbols).

[1] M. Tsuji et al. Chem. Phys. Lett. 355, 101 (2002).
[2] Y. Wada et al. Eur. Phys. J. D 66, 322 (2012).
[3] T. Wakabayashi et al. Carbon 50, 47 (2012).
[4] U. Szczepaniak et al. J. Phys. Chem. A 122, 89 (2019), and references therein.
[5] N. Kitamura et al. 1P-36, FNTG56, Tokyo (2019).
[6] T. Wakabayashi et al. 2P-35, FNTG55, Sendai (2018).
Corresponding Author: T. Wakabayashi, Tel: +81-6-4307-3408, E-mail: wakaba@chem.kindai.ac.jp- 59 -

1P-16
CuCl-Mediated Reaction of C60 with Propargylic Phosphate○Asumi Ishitsuka,1 Yutaka Maeda,1 Michio Yamada1
1

Department of Chemistry, Tokyo Gakugei University, Koganei, Tokyo 184-8501, Japan

Open-cage fullerenes have been attracted special interest not only as scaffolds formolecular containers in host-gest chemistry but also as precursors for endohedral fullerenes
encaging small atom(s) or molecule(s) [1]. Recent studies have also showed that open-cagefullerenes are applicable for electron-accepting materials in organic photovoltaic devices [2].
Recently, we have demonstrated that transition-metal-catalyzed reactions of C60 andpropargylic esters provided formal [2+2] and [4+2] cycloadducts via cyclization of the
carbonyl group and the activated C–C triple bond of the propargylic ester in the 6-endo-dig
mode followed by cycloaddition to C60 [3]. During this study, we encountered an
unprecedented formation of open-cage fullerenes via a one-pot CuCl-mediated reaction of C60
with easily accessible propargylic phosphate. In this presentation, we show that
CuCl-mediated reaction of C60 with 1,1-dimethylprop-2-yl diphenyl phosphate (1) affords 2, 3,
and 4 (Scheme 1). Notably, the yields of 2 and 4 depend strongly on the reaction conditions
employed. Results also suggest that the reaction involves the formation of the phosphate to
the 1,3-dienyl phosphate, which enables the reaction with C60 by [4+2] cycloaddition to form
the cyclohexene-annulated intermediate and subsequent intramolecular syn elimination of thephosphodiester affords 2 as the precursor for 4. The transformation of 2 to 4 can be explainedby invoking the intramolecular [4+4] cycloaddition followed by retro-[2+2+2] cycloaddition
sequence [4].

Scheme 1. CuCl-mediated reaction of C60 with 1.
[1] For selected reviews, see: (a) Y. Rubin Chem. Eur. J. 3, 1009 (1997). (b) K. Komatsu et al. Chem. Lett. 34,
886 (2005). (c) S.-i. Iwamatsu et al. Synlett 14, 2117 (2005). (d) M. Murata et al. Chem. Commun. 46, 6083
(2008). (e) L. Gan et al. Adv. Mater. 22, 1498 (2010). (f) G. C. Vougioukalakis et al. Chem. Soc. Rev. 39, 817(2010). (g) Y. Li et al. Chem. Eur. J. 23, 10485 (2017).
[2] (a) M. Murata et al. Chem. Commun. 47, 7335 (2011). (b) C.-P. Cheng et al. Adv Energy Mater. 1, 776(2011).
[3] (a) M. Yamada et al. Org. Biomol. Chem. 15, 8499 (2017). (b) M. Yamada et al. J. Org. Chem. 84, 9025
(2019).
[4] M.-J. Arce et al. J. Am. Chem. Soc. 118, 3775 (1996).
Corresponding Author: M. Yamada
Tel: +81-42-329-7493, Fax: +81-42-329-7493
E-mail: myamada@u-gakugei.ac.jp- 60 -

1P-17
Catalytic activity for reduction of 4-nitrophenol using on gadolinium(III)oxide nanoparticle-[C60]fullerene nanowhisker composites○Jeong Won Ko1, Sugyeong Jeon2, Weon Bae Ko1,2,3
1

Nanomaterials Research Institute, 2Department of Convergence Science, Graduate School,3
Department of Chemistry, Sahmyook University,,
815 Hwarang-ro, Nowon-gu, Seoul 01795, Republic of Korea

Ethylamine (C2H5NH2) was added to containing an aqueous solution of gadolinium nitratehexahydrate (Gd(NO3)3·6H2O) under vigorous stirring condition. The precipitated solution
was heated at 120 °C for 12 h in an oven. The resulting mixture was centrifuged several times
and then washed with distilled water to obtain gadolinium hydroxide. The product was driedat 80 °C in an oven. Gd(OH)3 was annealed to obtain Gd2O3 in an electric furnace at 700 °C
for 4 h under argon atmosphere [1]. Gadolinium(III) oxide nanoparticle-[C60]fullerene
nanowhisker composites were synthesized using gadolinium(III) oxide nanoparticle solution,
C60-saturated toluene and isopropyl alcohol by the liquid liquid interfacial precipitation (LLIP)
method [2]. The final product of gadolinium(III) oxide nanoparticle-[C60]fullerene
nanowhisker composites was characterized by X-ray diffraction, scanning electron
microscopy, Raman spectroscopy, and transmission electron microscopy. The catalytic
activity of their hybrid nanocomposites was investigated in the reduction of 4-nitrophenol by
UV-vis spectroscopy. The kinetics study of catalytic activity for reduction of 4-nitrophenol
was followed a pseudo first-order reaction.
1.2

4-nitrophenol
0 min
2 min
4 min
6 min
8 min
10 min
12 min14 min16 min18 min20 min

0.8
0.0

0.6

-0.4
-0.8
-1.2

ln (C/C0)

Absorbance (a.u.)

1.0

0.4

-1.6
-2.0
-2.4
-2.8

0.2

-3.2
-3.6
-4.0

0.0
200

-0.18693 ± 0.01055
0.97211Slope
R-Square (COD)

0

2

4

6

8

10

12

14

16

18

20

Time (min)

300

400

500

600

700

800

Wavelength (nm)Fig.1 UV-vis spectrum and kinetics study for reduction of 4-nitrophenol withgadolinium (III) oxide nanoparticle-[C60]fullerene nanowhisker composites[1] J. Kang, B. Min, Y. Sohn, Ceram. Int. 41, 1243-1248 (2015).
[2] K. Miyazawa et al. Surf. Eng. doi.org/10.1080/02670844.2017.1396779 (2017).
Corresponding Author: W. B. Ko
Tel: +82-2-3399-1700, Fax:, +82-2-979-5318,
E-mail: kowb@syu.ac.kr- 61 -

1P-18
Reactions of S-Heterocyclic Carbenes with Fullerenes: Preparation
and Characterization of Dithiomethano-derivatives○Yuta Maeda1, Shinji Kanzawa1, Masahiro Kako*,1, Michio Yamada2, Yutaka Maeda2,
Makoto Furukawa3, Takeshi Akasaka*,2,3,4
Department of Engineering Science, The University of Electro-Communications,
Chofu 182-8585, Japan2
Department of Chemistry, Tokyo Gakugei University, Tokyo 184-8501, Japan
3
Foundation for Advancement of International Science, Tsukuba, Ibaraki 305-0821,
Japan
4
School of Materials Science and Engineering, Huazhong University of Science andTechnology, Wuhan, Hubei 430074, P. R. China
1

Endohedral metallofullerenes (EMFs) have been the focus of extensive researchbecause of their remarkable structures and properties. To date, a number of studies havebeen carried out to develop exohedral functionalization of EMFs, which will open up
various applications such as molecular electronics and biomedicines.
The methano-bridge formation is one of the most frequently employed reactions forfunctionalization of EMFs. Until now, many methanofullerenes have been reported using
the Bingel-Hirsch reaction, reactions of carbenes and diazoalkanes, electrochemical
synthesis, the radical malonate addition, and zwitterion addition.[1] For example,
M3N@Ih-C80 (M = Sc, Y, and Lu) reacted with carbenes to afford two regioisomeric
methanofullerenes.[2] As a part of our continuing study on the carbine addition offullerenes, we previously reported the reaction of a S-heterocyclic carbene (SHC)[3] with
C60 to produce the corresponding [6,6]-closed methanofullerene. Nevertheless, thesynthetic efficiency of the precursor of the SHC was not sufficient to study the propertiesof SHCs. Although N-heterocyclic carbenes (NHCs) have been extensively studied forthe application to catalysts or ligands for metallic complexes, examples of cyclic carbenes
containing other heteroatoms such as phosphorus and sulfur are extremely sparsecompared with those of NHCs.
We now report the methano-derivatives of fullerenes using novel SHCs generated bysynthetically more accessible precursors. The reaction of disilene to CS2 produced thecorresponding SHC 1, which reacted with Sc3N@Ih-C80 to afford the corresponding [6,6]open methano-bridged derivative 2.[4] Similar SHC derivatives were also obtained for C60
and C70. The details of electronic properties of these adducts will be discussed on thebasis of electrochemical measurements and the density functional theory calculations.
Scheme 1.

Mes2SiMes =SiMes2

Scheme 2.

CS2

S
S

Mes2SiS

SiMes2

SiRMes2
S

1

SiMes2
1

Sc3N@Ih-C80

Partial structure of 2

[1] M. Yamada et al. Chem. Rev. 113, 7209–7264 (2013). [2] M. Yamada et al. Chem. Eur. J. 23, 6552–
6561 (2017). [3] H. Nikawa et al. Angew. Chem. Int. Ed. 117, 7739–7742 (2005). [4] M. Kako, et al. Helv.
Chim. Acta 102, e21477 (2019).
Corresponding Author: Masahiro Kako Tel: +81-42-442-5570. E-mail: kako@e-one.uec.ac.jp- 62 -

1P-19Research of Fracture Behavior of CNT/HDPE Composites via Melt
Blending○Koichi Utsugi1, Nao Otsuki1, Masaru Sekido2
Advanced Course of Production System Engineering, National Institute of Technology,
Sendai College, Natori 981-1239, Japan2
Department of Materials and Environmental Engineering, National Institute of Technology,
Sendai College, Natori 981-1239, Japan
1

CNTs are considered as the ideal reinforcement fillers for the nanocomposite materials due totheir outstanding mechanical properties, such as tensile strength, light weight, and low density.
Last year we have reported tensile strength of CNT/high density polyethylene (HDPE)
composites prepared by Melt Blending. As a result, the fracture strain decreased as the weightratio of CNTs was increased [1]. Aggregation of CNTs was not observed from the composite[2]. In this work we investigated the reason why the fracture strain of CNT/HDPE composites
was decreased by observing the crystal state of HDPE.
In this report the crystal state of HDPE was studied using a differential scanning calorimetry(DSC) to measure crystallinity of the composite. The difference between thermal analysis ofcross section and fracture surface depending on the different weight ratio of CNT/HDPE wasmeasured by DSC (Fig. 1). Crystallinity of HDPE increased as the weight ratio of CNTs wasincreased. Crystallinity of 4.8wt.% MWNT composites was 2.7% higher than 2.9wt.% MWNT
composites. It is suggested that the cause of the decrease in fracture strain is not due todecreased of the crystallinity for base material.
0.00

-0.10
-0.20

mJ/mg

-0.30
-0.40
-0.50
-0.60
-0.70
-0.80

20

40

60

80

ºC

100

120

140

Fig. 1 DSC chart of cross section for MWNT/HDPE composites. gray is 2.9wt.%MWNT. black is 4.8wt.%MWNT.
[1] Atsushi Onodera et al., The 54th fullerenes-Nanotubes-Graphene General Symposium, 1P-11(2018)[2] Koichi Utsugi et al., The 56th fullerenes-Nanotubes-Graphene General Symposium, 2P-19(2019)
Corresponding Author: Koichi Utsugi
Tel: +81-22-381-0329, Fax: +81-22-381-0329
E-mail: a1912605@sendai-nct.jp- 63 -

1P-20Preferential stability of carbon nanotubes with sub-nm diameter underlinearly polarized laser irradiation: An ab initio TDDFT study○Yoshiyuki Miyamoto1
1

Research Center for Computational Design of Advanced Functional Materials, National
Institute of Advanced Industrial Science and Technology (AIST), Central 2, 1-1-1 Umezono,
Tsukuba 305-8568, Japan
Carbon nanotubes (CNTs) with diameters less than 1 nm are thermally [1] and chemically[2] unstable compared to those with larger diameters. However, in this work, survival of suchthin CNTs under irradiation with ultra-short pulse laser is demonstrated. Diameter thinning of
CNTs by laser shot was reported [3], and those CNTs contained vacancies which resulted instructural defects after the thinning. On the other hand, this work targets vacancy-free CNTs.
For demonstrating the preferable stability of thin CNTs, first-principles molecular dynamics(MD) simulation based on the time-dependent density functional theory (TDDFT) was
performed under a laser irradiation by using fictitious model of one-dimensional alternatingarray of (8,0) and (14,0) CNTs or (5,5) and (8,8) CNTs. When polarization of the laser field is
set perpendicular to tube axes, the CNTs with larger diameters are destroyed while those withsmaller diameter survive, as seen in snapshot ofFig. 1 for a case with (8,0) and (14,0) CNTs [4].
The assumed laser conditions were thepulse-width 10 fs, wavelength 800 nm, and the
maximum field intensity 5 V/Å withcorresponding fluence 3.32 J/cm2.
The background physics of this selection ispolarization direction of the laser field that Fig.1 Snapshot of TDDFT-MD simulation of
makes the tangential area of CNT wall along (8,0) and (14,0) CNT arrays under laser shotwith the laser field larger with larger diameters. with a polarization as indicated by a verticalarrow in the left most panel.
More details will be discussed in thepresentation of this work.
This work was performed with support from the NEDO project “Development of advanced
laser processing with intelligence based on high-brightness and high-efficiency laser
technologies” (TACMI project).
[1] M. Terrones, et al. Science, 288, 1226 (2000).
[2] W. Zhou, et al. Chem. Phys. Lett 350, 6, (2001).
[3] Y. Zhang, Z. Shi, Z. Gu, and S. Iijima, CARBON, 38, 2055 (2000).
[4] Y. Miyamoto, in preparation.
Corresponding Author: Y. Miyamoto
Tel: +81-29-849-1498, Fax: +81-29-861-3171,
E-mail: yoshi-miyamoto@aist.go.jp- 64 -

1P-21Synthesis of carbon nanotubes on nanozirconia-dispersed carbon paper○Dai Goudo, Nobutomo Yamaguchi, Kiyofumi Yamagiwa
Graduate School of Science & Engineering, Teikyo University of Science,
Adachi, Tokyo 120-0045, Japan
Carbon nanotubes (CNTs) are promising for use in electrode materials, such as conductive
agents and catalyst supports, because of their morphological characteristics and highconductivity. Electrodes are generally produced by coating a substrate (e.g., carbon paper(CP)) with a slurry of the electrode material. A typical drawback of CNTs as electrodematerials is their low dispersibility in the slurry, leading to localization of CNTs on theelectrodes. This drawback can be addressed by homogeneous direct synthesis of CNTs on CP,
which can also result in improvements to the electrode surface area. In this study, CNTs weresynthesized on CP by chemical vapor deposition (CVD) with camphor. In particular, zirconia
nanoparticles (nanozirconia) were dispersed on the surface of CP before the synthesis to
examine its effects on CNT growth.
Small pieces of CP (Toray TGP-H-120) were dipped in 0.3% and 30% nanozirconia
dispersion liquid, and used as substrates after drying (0.3%-Zr/CP, 30%-Zr/CP, respectively).
CVD was carried out using camphor (C10H16O) and ferrocene as the carbon source and thecatalyst precursor, respectively. The syntheses were performed at 750°C for 15 min underflowing Ar gas.
In the case of as-supplied CP as the substrate, a small quantity of carbonaceous material
was deposited inhomogeneously on the surface. In contrast, when 0.3%-Zr/CP was used as thesubstrate, a large number of
CNTs were observed, as shownin Fig. 1. This result indicatesthat the formation of Fe catalyst
nanoparticles from ferrocene waspromoted by the effects ofdispersed nanozirconia on thesurface. However, no specificproduct was confirmed in thecase of 30%-Zr/CP, suggestingthat a moderate amount ofnanozirconia dispersed on thesurface is critical for thepromotion of CNT growth.
Detailedcharacterizations,
includingelectrochemical
characteristics, will be discussed Fig. 1. Scanning electron microscopy image of CNTs grown on
in the presentation.
nanozirconia-dispersed carbon paper.

Corresponding Author: K. Yamagiwa
Tel: +81-3-6910-1010
E-mail: yamagiwa@ntu.ac.jp- 65 -

1P-22
Scalable Synthesis of Atomically Precise Graphene Nanoribbons
in Metal–Organic Framework○Takashi Kitao1,2, MacLean W A Michael2, Kazuki Nakata2, Takashi Uemura1,2,3
1

Graduate School of Engineering, The University of Tokyo, 5-1-5 Kashiwanoha, Kashiwa,
Chiba 277-8561, Japan
2
Graduate School of Frontier Sciences, The University of Tokyo, 5-1-5 Kashiwanoha,
Kashiwa, Chiba 277-8561, Japan
3
CREST, Japan Science and Technology Agency (JST), 4-1-8 Honcho, Kawaguchi, Saitama
332-0012, Japan
Graphene nanoribbons, defined as nanometer-wide stripes of graphene, have attracted
significant attention as candidates for next-generation semiconductor materials. The structuralperfection of GNRs is an essential issue because their physical properties are criticallydependent on nanoribbon’s width and edge geometry. In this regard, simple and effective
fabrication methods for atomically precise GNRs should be developed not only for
fundamental research but also for their future applications in advanced opt-electronic devices.
However, the widespread implementation of GNRs into the various devices has yet to berealized, as methods for the synthesis of GNRs in precise and scalable fashion are currently
lacking.
Metal–organic frameworks (MOFs), porous materials formed through the self-assembly of
metal ions and organic ligands, have been applied to a variety of applications, including gas
storage, separation, and catalysis. MOFs have the advantages of the tunable and regulated
nature of their nanospaces and have been shown to provide an ideal compartment forcontrolling the arrangement of guest species through the geometrical constraint of host pores,
as well as non-covalent interactions between host and guest.[1] Here, we exploited a new
method that circumvents the issues surrounding the synthesis of GNRs utilizing the MOFs as
a template. A series of characterizations of the GNR, including NMR, UV/vis/NIR, andRaman spectroscopy measurements, confirmed the formation of the GNR withwell-controlledcontrolled edge structure and width (Fig. 1).[2]Fig. 1. Schematic image for preparation of an atomically precise GNR using a MOF as template.
[1] T. Kitao, T. Uemura et al. Chem. Soc. Rev. 2017, 46, 3108-3133.
[2] T. Kitao, T. Uemura et al. submitted.
Corresponding Author: T. Kitao
Tel: +81-4-7136-3791, Fax: +81-4-7136-3792,
E-mail: kitao@edu.k.u-tokyo.ac.jp- 66 -

1P-23
Direct precipitation growth of multi-layer graphene using W capping layer-Dependence of growth atmosphere○Jumpei Yamada1, Yuki Ueda1, Takahiro Maruyama2, and Shigeya Naritsuka1
1

Department of Materials Science and Engineering, Meijo University,
Nagoya 468-8502, Japan2
Department of Applied Chemistry, Meijo University, Nagoya 468-8502, Japan

Recently, graphene growth on an insulating substrate has been frequently
studied as an alternative method without using the transfer process. We havesucceeded in the direct growth of multilayer graphene using a W capping layer ina high vacuum [1]. In this study, in order to develop its application fields, a precipitation
method was also studied at atmospheric pressure.
W(20nm) / a-C(5nm)/ Ni(300nm) layers were deposited on a sapphire substrateusing electron-beam deposition. These samples were annealed at 900 oC for 30minin atmospheric pressures of nitrogen (N2:1000 [ml/min]) and nitrogen andhydrogen mixed gas (N2:1000 [ml/min]+H2:20 [ml/min]). After the annealing, thecatalyst layers were removed to directly obtain the graphene on the substrate.
Fig.1 (a) shows the Raman spectrum of the sample annealed under N2
atmosphere without graphene signals. The catalytic metals were observed to beoxidized by the residual oxygen in the ambient. As a result, graphene did not grow.
In contrast, in the case of mixed gas, multilayer graphene was directly grown on
the substrate. The G and G '(2D) peak were observed on the Raman spectra in
Fig.1 (b), which indicates graphene was successfully precipitated on the substrate.
This is probably because the mixing hydrogen was useful to suppress the etchingeffect of residual oxygen. Finally, we succeeded in the direct growth of multilayer
graphene at atmospheric pressure by using a mixed gas of N2 and H2.

Fig.1 Raman spectrum of grown samples with (a) unmixed N2 gas, and (b) mixed gas of N2 and H2
Reference: [1] J. Yamada et al. J. Appl. Phys. 55,100302 (2016).
Acknowledgement: This work was supported in part by JSPS KAKENHI Grant Numbers 2660089, 15H03558,
26105002, 25000011.
Corresponding Author: Jumpei Yamada, E-mail:jjjjjjyyyyyy119@gmail.com- 67 -

1P-24
NOx adsorption dynamics on Nanographene assembly system○Y.Hikage1, S.Nishijima1, K.Takai1,2
12Graduate school of Science and Engineering, Hosei University, Tokyo 184-8584, Japan
Department of Chemical Science and Technology, Hosei University, Tokyo 184-8584, Japan

Activated Carbon Fibers (ACFs) consisting of 3D random network of nanographenes having
localized spins induced by the edge-state on the zigzag part of its periphery are useful to remove
removing NOx pollutants due to its chemical activity and nanopore between nanographenes
giving high specific surface area [1, 2]. The major species in the vicinity of the source of NO xsuch as coal-fired power plants is NO molecule having spin moment (S=1/2). In this study, NO
adsorption and chemical reactivity in ACFs under atomospheric condition are evaluated in termsof the presence of ambient water molecule adsorbed inside nanopore, whre the spin magnetism
is used as a prove to track the adsorption daynamics of NO molecule into ACFs.
ACFs (FR-20, Kuraray) was vacuum-heated at 473 K for 30 min at 10-4 Pa (ACF-HT) andNO gas was introduced at a partial pressure of 2 kPa (ACF-NO), followed by evacuation down
to 10-4 Pa (ACF-NO-VAC). XPS, SEM-EDS were measured by Phi5600 and SU8020,
respectively. X-band ESR and SQUID magnetometer measuremernts are carried out by JEOL
FA-300 at room temperature and QD-MPMS-1 at 2 - 300 K under 0 - 10000 Oe.
SEM image and EDS mapping of the fracture surface of ACF-NO confirmed adsorbed NO
exist as nitrogen compounds uniformly distibuted inside ACFs as well as the surface (Fig. 1 (a)(b)). In the XPS N1s spectrum shown in Fig. 1 (c), the peak derived from NO3 clealy emerges
after NO adsorption. Fig. 2 shows the magnetization curves of ACF-HT and ACF-NO-VAC.
By adsorption NO, the magnetization is reduced by 39%, which is similar to the difference inthe ESR intensity for ACF-HT and ACF-NO-VAC. This indicates that ACFs and NO ischemically bond and cancel the edge-state spins. However, linewidth of the ESR spectrum
increases sharply at the instance of the introduction of NO molecules due to dipolar interactions
between edge-state spins of ACFs and adsorbed NO molecules, suggesting the physisorption of
NO moleucle at the initial stage of the adsorption.
[1] T. Shimohara et al, J. Jpn. Soc. Atmospheric Env., 48, 65-73 (2013).
[2] Fujita et al, J. Phys. Soc. Jpn, 65, 1920-1923 (1996).

(a)

(c)

N 1s

EDS

(b)

Intensity (arb. unit)

ACF - NOACF - HT
395
O 1s

405

(d)

415

ACF-NO

Magnetization (emu / g)

SEM

ACF - HT
520
10 µm

530
Binding energy (eV)

0.025

0

0

5000

10000

540

Fig. 1 SEM and EDS images after NO adsorption and
XPS spectra about ACF-HT (○) and ACF-NO (●)
Corresponding Author: Kazuyuki Takai
Tel: +81-42-387-6138, Fax: +81-42-387-7002

0.050- 68 -

Magnetic field (Oe)Fig. 2 Magnetic susceptibility
for ACF-HT (▲) and ACF-NO-VAC (■)

1P-25
Correlation between chemical structure and catalytic activity of graphene oxide○Ryutaro Suzuki1, Takuya Isaka1, Kentaro Tajima1, Kana Nakahara2, Yoshiaki Matsuo3,
Nobuyuki Akai2, Kazuyuki Takai1
1

Hosei Univ., 2Tokyo Univ. of Agric. and Tech., 3Univ. of Hyogo

In this study, two kinds of graphene oxide (HGO andTable 1 Amount of π conjugation
BGO) was synthesized by the Hummers [1] andof HGO and BGO
Brodie [2] methods respectively, and the correlation
between their chemical structure and chemical
Sampleπ conjugation (g / L)
activity was evaluated. Previous studies have shown
HGO
2.61
that HGO has many carboxy and hydroxy groups, and
BGO
0.62
BGO has many epoxy groups [3]. When the epoxy
group is introduced, the symmetry of the AB
Graphite
4.56
sublattice of graphene is maintained, but thesymmetry is broken in the case of attaching the hydroxy group or carboxy group, because theybond to only one of the AB sublattice sites. Therefore, the electronic state that causes the
localized spin magnetism appears in the Fermi energy (EF), suggesting that the catalytic activityof HGO, BGO was significantly different. In this study, an amine oxidation coupling reaction
to obtain N-Benzylidenebenzylamine from Benzylamine was carried out with adding HGO andBGO as catalyst to evaluate the chemical activity of GOs.
HGO and BGO was synthesized by the Hummers method in which graphite is oxidized using
concentrated sulfuric acid and potassium permanganate, and Brodie method using fuming nitricacid and potassium chlorate, respectively.
The oxidative coupling reaction of amine was performed by adding HGO (BGO) sample asa catalyst to Benzylamine and stirring for 24 h while heating at 60 °C to synthesize NBenzylidenebenzylamine.
Table 1 shows the amount of π-conjugated system in GO dispersion obtained by using
empirical formula [4], which can evaluate the amount of π conjugated system of GO from theabsorbance of UV-vis measurement at 660 nm. The π conjugated systems were more destroyedin BGO than those in HGO. This proved that the oxidationby the Brodie method had more epoxy groups that formed more sp3 bonds that destroyed the πconjugated system.
Table 2 shows the conversion of Benzylamine and the molar ratio of a by-product,
Benzaldoxime. HGO catalyst has lower Benzaldoxime yield despite higher Benzylamine
conversion than BGO catalyst. Thus, HGO and BGO
follow different reaction pathways based on the Table 2 Molar ratio of byproduct andstructural difference. Investigation of the correlation Conversion for HGO and BGO catalyst
between active species in graphene oxide and catalytic
activity in this way can enable the invention of a new
Catalyst
GC-Yield
Conversion (%)
green catalyst with selectivity.
[1] D.C. Marcano et al, ACS Nano, 4, 4806 - 4814 (2010)(Molar ratio)[2] B.C. Brodie, Phil. Trans. R., Soc. Lond., 149, 249 - 259(1859)[3] K.Tajima et al, Polyhedron, 136, (2017)[4] Coleman et al, Nat. Nanotechnol September, 3 (2018)- 69 -

HGO

1

40

BGO

2.8

26

No catalyst0-1P-26
Investigation of surface potential variations of thermally reduced graphene
oxide○K. Kanishka H. De Silva, Shuhei Ogawa, Pamarti Vishwanath, Masamichi Yoshimura
Graduate School of Engineering, Toyota Technological Institute, Nagoya 468-8511, Japan
Fabrication of graphene by the reduction of graphene oxide (GO) is one of the most widely
studied topics due its ability of bulk production of graphene with controllable properties thatcan be assigned to a vast range of applications [1]. Investigation of local electronic propertiesof graphene and its derivatives, such as work function (WF) and surface potential (SP), is
necessary for applications based on electronic devices. Kelvin probe force microscopy(KPFM) is widely used for mapping the surface potential of graphene-based materials [2].
However, depending on the properties of graphene and GO, such as amount of oxygen
containing groups, number of layers, and heteroatom doping, and also on KPFM
measurement conditions (humidity, mode of measurement, etc.), WF and SP values show adiscrepancy [3]. Here, we focus on the SP variation of GO sheets upon thermal reduction bycarrying out the KPFM measurements under same environmental conditions. For comparison,
KPFM measurement of pristine graphene grown by chemical vapour deposition was also done
(not shown here).
The GO flakes were deposited on SiO2 (300nm)/Si substrates (S) by spin coating. Thermal
annealing of GO was done at 800 oC for different
times such as 5 min, 10 min, 20 min, and 30 min.
Then, topography and the SP were measured at
the same place and the WF was calculated.
Figures 1(a) and 1(c) show the atomic force
microscopic (AFM) height images of GO and GO
after annealed for 5 min. The layers (L1, L2, L3)
have been preserved after the thermal treatment
except for the reduction in thickness from 1 nm to
0.4 nm due to the removal of oxygen
functionalities. Figures 1(b) and 1(d) are the Fig.1. AFM height and potential images of GO
corresponding potential images. In the potential (a and b) and GO after annealed for 5 min (cimage of GO, there is no clear contrast among and d).
layers due to its insulating nature associated by oxygen functionalities. In contrast, even after
5 min of annealing, difference in potential of L1 and L2 is clearly visible (L2 is outlined)
indicating the change in electronic properties. However, L3 cannot be seen clearly because of
the screening effect [2]. The calculated WF of L1 was varied from 5.38 eV to 4.75 eV after
annealing for 5-30 min. These results demonstrate that graphene with tunable electronic
properties can be obtained by controlling the reduction conditions.
[1] K.K.H. De Silva et al. Appl. Surf. Sci. 447, 338 (2018).
[2] Lee et al. Appl. Phys. Lett. 95, 222107 (2009)[3] V. Panchal et al. Sci. Rep. 3, 2597 (2013)
Corresponding Author: K.K.H. De Silva
Tel: +81-52-809-1852
E-mail: sd16501@toyota-ti.ac.jp- 70 -

1P-27
Adsorption effects of molecular Hydrogenon the electronic transport properties of Graphene○Y. Shigehisa1, Y. Obata1, Y. Ishiguro2, K. Takai1, 2
12

Dept. Applied Chemistry, Hosei University, Tokyo 184-8584, Japan
Department of Chemical Science and Technology, Hosei University, Tokyo 184-8584, Japan

Molecular hydrogen adsorption is one of the most important examples in terms of applications
for the transistor devices accompanied with band gap opening technology and hydrogen storage
materials. Meanwhile, defect-introducing is one of the interesting strategies to give additional
adsorption sites to graphene in view of enhancing the interactions between hydrogen andgraphene [1]. In this study, we investigated carrier doping and scattering caused by molecularhydrogen adsorption before and after defect-introducing into graphene by Ar+ beam irradiation
by means of electric conductivity measurement.
A field effect transistor using graphene obtained by exfoliation of graphite (g-FET) was
fabricated on SiO2 / Si substrate. Time dependence of the electrical conductivity for the g-FET
was measured after annealing in a vacuum chamber followed by hydrogen adsorption (1 atm)
at room temperature (NoDefect). For defect-introduced graphene, atomic vacancies wereintroduced into the surface of g-FET by Ar+ beam irradiation at 100 eV after annealing,followed by exposing to hydrogen molecules (Defect+H2).
The charge neutral point (VCNP) where the minimum conductivity appears in a g-FET exhibits
no significant shift from 0.5 h after the molecular hydrogen adsorption up to 6 h (NoDefect).
In contrast, VCNP shift by molecular hydrogen adsorption on defect-introduced graphene was 25 V (Defect+H2). Moreover, VCNP shift by following evacuation was very small (Vacuum).
The observed shifts indicate the strong chemical adsorption by molecular hydrogen adsorption.
These results suggest that defect-introducing to graphene is important to provide additional
adsorption sites for efficient molecular doping.
[1] G. Sunnardianto,et al, Int. J. Hydrogen Energy, 43 (2017).

0.035

Vacuum

0.03
0.025

10

PristineΔVCNP (V)

Conductivity (mS)

0.04

Defect+H2

-60

0
-10
-20
-30

-30
0
30
Gate Voltage (V)Fig. 1 Effects of H2 adsorption on the transfer+
curve of g-FET that irradiated by Ar beam

- 71 -○ Pristine□ NoDefect× Defect+H2▲ Vacuum

050Time (h)100Fig. 2 Time evolution of ΔVCNP upon
H2 adsorption and after evacuation

1P-28Multi-ferroic response of two-dimensional hexagonal materials
F. R. Pratama1, M. S. Ukhtary1, R. Saito1
1Department of Physics, Tohoku University, Sendai 980-8578, Japan
Two-dimensional (2D) hexagonal materials, such as silicene & MoS2 havepromising applications in next-generation electronics. Researches in themagnetic properties of the 2D materials are growing in the field of magnetoelectronics and spintronics to realize devices with low energy consumption [1,2].
Recently, a theoretical study on the magnetic susceptibility of massive 2D
Dirac systems in low temperature has been performed by Koshino and Ando [3],in which they found that the magnetic susceptibility is non-zero when the Fermi
energy is smaller than the band gap. This property appears due to the spin andvalley degeneracy in the Landau levels. However, in the case of silicene, theLandau levels are non-degenerate for each spin direction at the K and K’ valleys
due to the strong spin-orbit coupling. Moreover, the energy gap of silicene istuneable by an external electric field perpendicular to the 2D plane [4]. Thus, we
expect that the magnetic susceptibility can be controlled by the electric field.
In this study, we calculate the magnetic susceptibility of silicene for a given
temperature as a function of electric field. First, we show the formation of the
Landau levels around the K and K’ points as a function of the external electricand magnetic fields. By obtaining the Landau levels, we calculate thethermodynamic potential, magnetization, and magnetic susceptibility of thesystem. We expect to find the temperature range in which the magnetic
susceptibility can be effectively controlled by the electric field and address therole of spin-orbit coupling.
References:[1] A. M. Tokmachev et al, Nat. Commun. 9, 1627 (2018).
[2] M. Gilbertini et al, Nat. Nanotechnol. 14, 408 (2019).
[3] M. Koshino and T. Ando, Solid State Commun. 151, 1054 (2011).
[4] M. Ezawa, Phys. Rev. B 86, 161407(R) (2012).

- 72 -

1P-29Carrier-dependent photoluminescence properties of
CVD-grown monolayer MoS2
○Kana Kojima, Hong En Lim, Yusuke Nakanishi, Takahiko Endo, Yutaka Maniwa,
Yasumitsu Miyata
Department of Physics, Tokyo Metropolitan University, Hachioji, 192-0397, JapanThe optical properties of transition metal dichalcogenide (TMDC) atomic layers haveattracted much attention because of their unique spin-valley coupling and excitonic opticalresponses. Recently, Lien et al. has reported that the non-radiative relaxation of TMDC depend
strongly on various factors, which include supporting substrate and carrier density [1]. While
we have demonstrated that the growth substrates play a major role in non-radiative relaxationof chemical vapor deposition (CVD)-grown monolayer MoS2 [2], the effect of carrier density
remains unclear. In this work, we have investigated the carrier-dependent photoluminescence(PL) response of monolayer MoS2 grown on SiO2 by using electrostatic doping.
A simple field effect transistor device were fabricated to regulate the carrier density of themonolayer MoS2 by varying the backgate voltage (Vg). As shown in Fig. 1a, the increase ofnegative trions by such electron doping results in a red shifted PL peak with weakened
intensity at Vg=30 V [3]. The PL lifetime, in contrast, is insensitive to the different Vg appliedwith an approximate value of 20 ps (Fig. 1b). These results suggest that the carrier density has
only a minor contribution to the non-radiative relaxation of the MoS2 grown on SiO2. In thispresentation, we will also discuss the effects of carrier density and substrate on MoS2-based
van der Waals heterostructures.

Fig. 1. (a) PL spectra and (b) time-resolved PL decay profiles of CVD-grown monolayer MoS2 on SiO2 undergate voltages, Vg = –30, 0, 30V.
[1] D. H. Lien et al., Science 364 468-471 (2019) [2] K. Kojima et al., Nanoscale 11 12798-12803 (2019) [3] K.
F. Mak et al., Nat. Mater. 12 207-211 (2013)
Corresponding Author: Y. Miyata, Tel: 042-677-2508, E-mail: ymiyata@tmu.ac.jp- 73 -

1P-30Self-Assembly of Nanodiamonds through Soft Gel from their Solutions○Toshihiko Tanaka1,2, Yasuhiro F. Miura3, Tetsuya Aoyama2, Masaya Nemoto1,2,
Shusuke Ando1, Yuho Itabashi1, Kazunori Miyamoto4, Atsuya Muranaka2,
Masanobu Uchiyama2,4, Eiji Osawa5
1

Department of Chemistry and Biochemistry, National Institute of Technology,
Fukushima College, 30 Aza-nagao, Tairakamiarakawa, Iwaki, Fukushima, 970-8034, Japan
2
Elements Chemistry Laboratory, RIKEN Cluster for Pioneering Research,
2-1 Hirosawa, Wako, Saitama, 351-0198, Japan
3
Hamamatsu University School of Medicine, 1-20-1 Handayama,
Higashi-ku, Hamamatsu city, Shizuoka, 431-3192, Japan4
	  Graduate School of Pharmaceutical Sciences, the University of Tokyo,
7-3-1 Hongo, Bunkyo-ku, Tokyo 113-0033, Japan
5
Nano Carbon Research Institute Ltd., Asama Research Extension Center,
Shinshu University, 3-15-1 Tokida, Ueda, Nagano, 386-8567 JapanWe already reported two kinds of rectangular precipitates of detonation nanodiamonds(DND): one is a fine tape-like whisker1 and the other is a nanosheet2. We consider that one
interesting aspect of the self-assembly of DND is its application to the drug delivery systems3
for cancer therapy and that aggregated elementary diamond nanoparticles (~50nm) play aneffective role in avoiding serious side effects to hearts or to bone marrow through EPR effect4.
We demonstrate herein further results on the precipitates.
The whiskers are formed through the gelation of DND and a kind of crystallization takes
place from soft gel to hydrated colloidal crystals. Curved whiskers were precipitated on thewall of a test tube at the meniscus between air, glass and DND solutions. The meniscus wasmoving down slowly (<1mm/h) through the evaporation of water in vacuum and theconcentrated solution became the gel because gelation takes place over 7wt.%. Their
rectangular shapes depend on the concentration of the solution. If a DND solution of over 4
wt.% dries out in the tube, a ring of a long-curved whisker can be removed easily after drying.
They were slightly elastic, being able todeform a little without breaking and havebirefringence (Fig.1).
The nanosheets were crystallized from adiluted DND solution on a Langmuirmonolayer of arachidic acid (AA) and we
consider that they include the monolayer.
The horizontal lifting technique allows us
to transfer the floating DND/AA hybrid
layer onto solid substrates any number oftimes, in such a way that a multi-layered
structure of the nanosheets can be
Fig.1 A ring of a curved DND whisker (φ~7mm):
constructed. Hence the nanosheets are (a)pending 2 rings; (b) an image with no nicols;amphiphilic because of the AA monolayer.	
  (c) that with	  cross	  	  nicols.
[1] E. Osawa; Diam.Rel.Maer. 16, 2018(2007);[2] T.Tanaka, Y.F. Miura, T. Sato, E. Osawa; Abstract of the 53th FNTG Symposium, 66(2017); [3] E.K.Chow,
X.-Q. Zhang, M. Chen, R. Lam, E. Robinson, H. Huang, D. Schaffer, E. Osawa, A. Goga, D. Ho, Sci. Trans.
Med., 3.73(2011); [4] Y. Matsumura. H. Maeda, Cancer Res., 46, 63872 (1986).
Corresponding Author: Eiji Osawa/Tel: +81--268-75-8381 / E-mail: osawa@nano-carbon.jp- 74 -

1P-31
Chemically synthesized ground state diatomic carbon (C2) serves as an
origin of carbon allotropes○Kazunori Miyamoto,1 Shodai Narita,1 Yui Masumoto,1 Takahiro Hashishin,1 Taisei Osawa,1
Mutsumi Kimura,2,3 Masahito Ochiai,4 Masanobu Uchiyama1,3,5
1

Graduate School of Pharmaceutical Sciences, The University of Tokyo, 7-3-1 Hongo,
Bunkyo-ku, Tokyo 113-0033, Japan
2
Division of Chemistry and Materials, Faculty of Textile Science and Technology, Shinshu
University, Ueda, 386-8567, Japan
3
Research Initiative for Supra-Materials (RISM), Shinshu University, Ueda, 386-8567, Japan
4
Graduate School of Pharmaceutical Sciences, University of Tokushima, 1-78 Shomachi,
Tokushima 770-8505, Japan.
5
Cluster of Pioneering Research (CPR), Advanced Elements Chemistry Laboratory, RIKEN,
2-1 Hirosawa, Wako-shi, Saitama 351-0198, Japan
Diatomic carbon (C2) exists in carbon vapour, comets, the stellar atmosphere, and interstellar
matter, but although it was discovered in 1857,[1] it has proved frustratingly difficult tocharacterize, since C2 gas occurs/exists only at extremely high temperatures (above 3500°C)(Fig. 1a).[2] Since 1930, several experimental methods to generate C2 have been developed byusing extremely high energy processes, such as electric carbon arc and multiple photon
excitation,[3] and the C2 species obtained werereported to exhibit singlet dicarbene (doublebond) and/or triplet biradical (triple bond)behavior.[4] In contrast, recent theoreticalsimulations suggest that C2 in the ground stateshould have a singlet biradical (quadruple bond)character (Fig. 1a).[5] Here, we present the first“chemical” synthesis of C2 in a flask at room
temperature or below, not only providing the firstexperimental evidence to support theoreticalpredictions that C2 has a singlet biradical
character with a quadruple bond, thus settling along-standing controversy between experimental
and theoretical chemists, but also achieving thefirst bottom-up chemical synthesis of carbon Fig.1 a) Long-standing dispute between
allotropes such as amorphous carbon, graphite,
experimental and theoretical chemists[6]
concerning the nature of diatomic carbon
carbon nanotubes, and C60 (Fig 1b).
(C2). b) Chemical generation of C2 and achemical synthesis of carbon allotropes.

[1] W. Swan, Trans. R. Soc. Edinburgh. 21, 411–430(1857). [2] G. Glockler, J. Chem. Phys. 22, 159–161 (1954). [3] P. S. Skell, et al. Acc. Chem. Res. 6, 97–105(1973). [4] P. S. Skell, et al. J. Am. Chem. Soc. 92, 5620–5624 (1970). [5] S. Shaik, Nat. Chem. 4, 195–199 (2012).
[6] K. Miyamoto, et al. ChemRxiv doi: 10.26434/chemrxiv.8009633.
Corresponding Author: K. Miyamoto, M. Uchiyama
Tel: +81-3-5841-0783, Fax: +81-3-5841-0733
E-mail: kmiya@mol.f.u-tokyo.ac.jp; uchiyama@mol.f.u-tokyo.ac.jp- 75 -

2P-1
Simple and Effective Method to Control Photoluminescence Properties ofSingle-walled Carbon Nanotubes by Ultrasonic Irradiation○Yui Konno1, Akane Nishino1, Michio Yamada1, Yutaka Maeda1, Saki Okudaira2, Yuhei
Miyauchi2, Kazunari Matsuda2, Jun Matsui3, Masaya Mitsuishi4, Mitsuaki Suzuki5
1

Department of Chemistry, Tokyo Gakugei University, Tokyo 184-8501, Japan
2
Institute of Advanced Energy, Kyoto University, Uji 611-0011, Japan3
Department of Material and Biological Chemistry, Yamagata University, Yamagata 9908560, Japan
4
Institute of Multidisciplinary Research for Advanced Materials, Tohoku University, Sendai
980-8577, Japan
5
Department of Chemistry, Josai University, Saitama 350-0295, Japan
It has been reported that the sidewall functionalization is effective to control the local band
structures of single-walled carbon nanotubes (SWNTs), resulting in emergence of new redshifted photoluminescence (PL) peaks in the near-infrared region [1,2,3]. This allows theexcitation with the E11 energy to afford increase of the PL excitation efficiency, which isadvantageous for bioimaging and so on. For the PL measurements, the use of low concentrated
and individually dispersed solution of SWNTs is preferred for avoiding concentrationquenching and unwanted interaction with other chiral SWNTs [4]. However, the sonication of
SWNTs is also known to shorten and damage the SWNTs [5,6]. Meanwhile, surfactant
decomposition has been studied and reported that the decomposition proceeds via generationof radical species from water upon ultrasonic irradiation [7]. Here we present the effects ofultrasonic irradiation on the PL properties of SWNTs under various conditions including
different surfactants, concentration of SWNTs, and atmospheres.
In this study, sodium cholate (SC), sodium dodecylbenzene sulfate (SDBS), and sodium
dodecyl sulfate (SDS) were selected as typical surfactants to disperse SWNTs in D2O. To clarify
the effect of ultrasonic irradiation, a small amount of SWNTs (initial concentration: 12.5 mg/L)
was sonicated and centrifuged to prepare the SWNTs dispersion. The characteristic absorption
and PL peaks of SWNTs were observed from thesupernatant prepared using SC. On the other hand, thesupernatant prepared using SDS exhibited low intrinsic
absorption and PL peaks of SWNTs. When SDBS wasused, the dispersibility of SWNTs was found to be as goodas that obtained with SC. In this case, it is noteworthy thatthe new PL peaks at 1043 and 1118 nm emerged
accompanied by decreasing the intrinsic PL peaks of
SWNTs, as seen in the oxidation of SWNTs [1, 2]. The
details of the control of the PL properties of SWNTs by Fig. 1 PL spectra of SWNTs dispersion.
Surfactant and sonication time areultrasonic irradiation will be discussed.
shown in the figure.

[1] R. B. Weisman et al. Science 330, 1656 (2010) [2] Y. Maeda et al. J. Am. Chem. Soc. 135, 6356 (2013) [3] Y.
Wang et al. Nat. Chem. 5, 840 (2013). [4] R. B. Weisman et al. Science 297, 593 (2002). [5] M. D. Lay et al. J.
Phys. Chem. C 114, 12490 (2010). [6] F. Hennrich et al. J. Phys. Chem. B 111, 1932 (2017). [7] M. Ashokkumar
et al. Aust. J. Chem. 56, 1045 (2003).
Corresponding Author: Y. Maeda
Tel: +81-42-329-7512
E-mail: ymaeda@u-gakugei.ac.jp- 76 -

2P-2
Stable MoO3 Doping of Carbon Nanotube Top Electrodes for Highly Efficient
Metal-Electrode-Free Perovskite Solar Cells
Seungju Seo1, Il Jeon1, Esko I. Kauppinen2, Yutaka Matsuo1,3, Shigeo Maruyama1,4
1. Department of Mechanical Engineering, School of Engineering, The University of Tokyo
2. Department of Applied Physics, Aalto University School of Science
3. Institutes of Innovation for Future Society, Nagoya University
4. Energy NanoEngineering Laboratory, National Institute of Advanced Industrial Science (AIST)

ABSTRACT
Organic-inorganic lead halide perovskite solar cells (PSCs), since the first report in 2009, haveattracted great interest for the high power conversion efficiency (PCE). Now the certified power
conversion efficiency (PCE) reads 25.2%. Accordingly, more research effort should be made on thedevice stability and the fabrication cost.
Top metal electrode in PSCs is usually thermally evaporated under vacuum. This substantially
increases the fabrication cost let alone the high cost of gold and silver. Furthermore, use of the metal
top electrodes deteriorates the long-term stability of PSCs as the metal ions migrate into the bulk of
the perovskite layer, undermining the device performance.
As an alternative to the metal electrodes, single-walled carbon nanotube (CNT) as the top electrodehas been reported to achieve high stability in PSCs owing to the hydrophobic nature of carbon andavoiding the ion migration. In addition, it drastically reduces the fabrication cost as it can be easily
deposited onto devices by a simple mechanical transfer. Despite such advantages, there are threefactors limiting the PCE of the CNT top electrode-based PSCs that need to be addressed: (1) the
unfavorable work function of the CNT with respect to the active perovskite layer, leading to loss involtage potential, (2) lower conductivity than the metal counterparts, limiting the fill factor (FF), and(3) less refractive nature with respect to incident light leading to loss in short-circuit current.
Here, we address those three issues by engineering the CNT top electrode. We tuned the work
function of CNT electrodes, increased their conductivity by depositing MoO3 under vacuum, without
damaging underneath perovskite layers. Using photoelectron yield spectroscopy, absorbance andraman spectroscopy, we determine the necessary MoO3 thickness and thermal annealing parameters toefficiently dope the CNT top electrode and study underlying doping mechanism between CNTs andMoO3 to achieve highly efficient CNT top electrode-based PSCs.
Corresponding Author: Prof. Shigeo Maruyama
Tel : +81)3-5841-6421
maruyama@photon.t.u-tokyo.ac.jp- 77 -

2P-3
Macrocyclic bis(dipyrrinato) metal complex for
single-walled carbon nanotube separation○ Guoqing Cheng, and Naoki Komatsu
Graduate School of Human and Environmental Studies, Kyoto University, Kyoto 606-8501,
Japan
We have been developing host-guest chemistry forseparation of carbon nanotubes (CNTs) according to theirstructure and physical properties. The host molecules named“nanotweezers” and “nanocalipers” has been designed andsynthesized to discriminate CNTs based on diameter,
metallicity and even handedness [1].
In this work, new nanocalipers with two dipyrrin moieties
at both ends were designed and synthesized. Dipyrrin
moieties with the parallel alignment formed the macrocyclic
homoleptic binuclear bis(dipyrrinato) metal complex in thepresence of copper ion. The resulting rigid macrocycle isFig.1 Schematic structure of the
expected to be able to interlock singlemacrocycle-interlocked SWNT
walled carbon nanotubes (SWNTs) with (a)a suitable structure (Fig. 1), andsimultaneously disperse SWNTs into thesolution phase.
In the extraction, nanocalipers and
HiPco SWNTs are bath-sonicated in thepresence of Cu(II) in THF. Aftercentrifugation, the resultant supernatant
was analyzed by absorption spectroscopy.
In Fig. 2a, upward shift of the baseline
and red-shift of the band around 460 nm
were observed, implying the extraction of
SWNTs and the complexation between(b)the macrocycle and SWNTs, respectively.
633 nm785 nmAfter demetallization followed bywashing out the host molecules
thoroughly, the resulting SWNTs wereanalyzed by Raman spectroscopy. At theexcitation of 785 nm, the content ofrelatively larger diameters (1.01-1.15 Fig.2 (a) Absorption spectra of the supernatant after 48 hnm) increase, while enrichment of sonication followed by centrifugation (gray trace) and thesemiconducting SWNTs is observed at macrocycle in THF (black trace). Inset: expansion at theregion of 800-1300 nm. (b) Normalized Raman spectra of
the excitation of 633 nm.
HiPco SWNTs before and after extraction (black and gray[1] G. Liu, N. Komatsu et al. J. Am. Chem.
traces, respectively) at 785 and 633 nm.
Soc., 135, 4805 (2013); J. Mater. Chem. A, 2,
19067 (2014); Org. Chem. Front., 4, 911 (2017).
Corresponding Author: Naoki Komatsu, Tel: +81-75-753-6833, E-mail: komatsu.naoki.7w@kyoto-u.ac.jp- 78 -

2P-4
Influence of the carbon-rich domain in hexagonal boron nitride ontransport properties of adjacent graphene○Momoko Onodera1, Kenji Watanabe2, Miyako Isayama1, Satoru Masubuchi1,
Rai Moriya1, Takashi Taniguchi2, and Tomoki Machida1,3
1

IIS, The University of Tokyo, Tokyo 153-8505, Japan
2
NIMS, Ibaraki 305-0044, Japan 3CREST-JST

Hexagonal boron nitride (h-BN) crystals synthesized under high pressure and hightemperature (HPHT) are known to have high quality and used in more than 200 research
institutes. However, all HPHT h-BN crystals have a distinct carbon(C)-rich domain at the coreregion, which contains a significant amount of C impurities. We found that this domain still
exists after exfoliation and cannot be identified with an optical microscope or AFM. To
evaluate the influence of the C-rich domain on adjacent graphene, we detected the C-richdomain by utilizing photoluminescence in UV range and fabricated graphene/h-BN
heterostructures with graphene placed across the boundary of the domain, which enabled us tomeasure graphene on the domain and pristine regions simultaneously. Graphene on the C-richdomain exhibited degraded carrier mobility and bending in the Landau-fan diagram [1]. The
plot of the energy at the bending point suggested the formation of an acceptor level located at
0.10 eV above the Dirac point. To elucidate the role of C impurities in h-BN, we also
conducted experiments using intentionally C-doped HPHT h-BN [2]. Graphene on C-doped
h-BN showed bending in the Landau fan diagram and strong hysteresis upon sweeping carrier
density, which further confirmed the existence of an acceptor state. Finally, we study h-BN
crystals synthesized at atmospheric pressure and high temperature (APHT) as an alternative to
HPHT h-BN [3]. We found that APHT h-BN does not have any distinct impurity-rich domains
and can be used as a high-quality substrate of other 2D materials.

Fig. 1: (a) SEM and (b) CL (320 nm) images of an HPHT h-BN crystal. (c) Optical microscope and (d) PL (340nm) images of an exfoliated HPHT h-BN flake. (e) Schematic and (f) photographic image of the device. (g)Temperature dependence of carrier mobility. (h) Extraction of charrier inhomogeneity n* at T = 2 K. (i) Rxx vs.
VBG at B = 0−9 T obtained in graphene on the C-rich domain. Data are offset in proportional to B for clarity.
[1] M. Onodera, K. Watanabe, M. Isayama, M. Arai, S. Masubuchi, R. Moriya, T. Taniguchi, and T. Machida,
Nano Lett. 19, 7282 (2019).
[2] M. Onodera, M. Isayama, T. Taniguchi, K. Watanabe, S. Masubuchi, R. Moriya, Y. Hoshi, T. Haga, Y.
Fujimoto, S. Saito, and T. Machida (submitted).
[3] M. Onodera, T. Taniguchi, K. Watanabe, M. Isayama, S. Masubuchi, R. Moriya, and T. Machida, Nano Lett.
20, 735 (2020).
Corresponding Author: M. Onodera
Tel: +81-3-5452-6158, Fax: +81-3-5452-6157, E-mail: monodera@iis.u-tokyo.ac.jp- 79 -

2P-5
Dielectric screening effects on photoluminescence of carbon nanotubes onhexagonal boron nitride○Nan Fang1,2, Keigo Otsuka1, Takashi Taniguchi3, Kenji Watanabe3, Kosuke Nagashio4,
Yuichiro K. Kato1,2
1

Nanoscale Quantum Photonics Laboratory, RIKEN Cluster for Pioneering Research,
Saitama 351-0198, Japan
2
Quantum Optoelectronics Research Team, RIKEN Center for Advanced Photonics, Saitama
351-0198, Japan
3
National Institute of Materials Science, Ibaraki 305-0044, Japan
4
Department of Materials Engineering, The University of Tokyo, Tokyo 113-8656, Japan
Hexagonal boron nitride (h-BN), a two-dimensional (2D)
material, is atomically flat with low defect density, which is
widely used to support other 2D materials. We expect that theadvantages of h-BN can also be utilized in mixed dimensional
heterostructures, and single-walled carbon nanotubes (CNTs)
would provide a unique opportunity in this context. The
one-dimensional nature of CNTs results in enhanced Coulombinteractions, giving rise to tightly bound excitons that show
photoluminescence (PL) at room temperature. CNTs directly
attached on solid-state substrates such as SiO2/Si, however,
suffers from the strong substrate quenching effect.[1] By usingh-BN as a substrate, the quenching effect is expected to be
suppressed. Moreover, excitons in CNTs are sensitive to thedielectric environment, and intimate contact with the h-BN could
result in large modifications in excitonic energies.
Here, we study h-BN effects on PL excitation (PLE) spectra of
Figure 1 PLE maps of an
CNTs by transferring h-BN flakes over air-suspended CNTs
[2]
air-suspended CNT before
grown over trenches on SiO2/Si substrates. Figure 1 shows PLE
and after the h-BN transfer.
maps of a suspended CNT before and after the h-BN transfer
with the excitation power fixed at 10 μW. Before the h-BN transfer, the values for the E11 andE22 are consistent with those for a (10,8) air-suspended nanotube. After the h-BN transfer, thePL intensity is decreased to approximately half of the initial value. This PL reduction causedby the h-BN flake is much weaker than that in the conventional SiO2/Si substrates. We also
observe redshifts in both E11 and E22 of 27 and 17 meV, respectively. Although the shift values
show tube-to-tube variations, all the CNTs show redshifts for both E11 and E22, which isconsistent with the dielectric screening effect from h-BN flakes.
Work supported by JSPS (KAKENHI JP19K23593, JP16H05962), MIC (SCOPE
191503001), and MEXT (Nanotechnology Platform). K. O. is supported by JSPS Research
Fellowship. We acknowledge the Advanced Manufacturing Support Team at RIKEN and T.
Nishimura for technical assistance.
[1] J. Lefebvre, Y. Homma, P. Finnie, Phys. Rev. Lett. 90, 217401 (2003).
[2] A. Ishii, M. Yoshida, Y. K. Kato, Phys. Rev. B 91, 125427 (2015).
Corresponding Author: Yuichiro K. Kato
Tel: +81-48-462-1449, Web: http://katogroup.riken.jp/, E-mail: yuichiro.kato@riken.jp- 80 -

2P-6
Synthesis of 3D hybrid Structures composed of Single-walled CNTs andMesopores Carbon by Chemical Vapor Deposition
Aliza Khaniya Sharma1, Kamal P Sharma1,2, Takahiro Saida1,2,
Shigeya Naritsuka3, Takahiro Maruyama1,2
1

Department of Applied Chemistry, Meijo University, Japan
2
Nanomaterials Research Center, Meijo University, Japan3
Department of Materials Science and Engineering, Meijo University, Japan
1. Introduction
It is highly desirable to obtain single-walled carbon nanotube (SWCNTs) and graphitic carbon
hybrid structure, which could open up the wider applicability as an electrode material in lithium ion
secondary battery with hybrid structure framework [1, 2]. In this study, to synthesize an SWCNTsgraphitic carbon hybrid structure, we carried out SWCNTs growth utilizing Co catalysts deposited on
mesoporous carbon (MC) by alcohol catalytic chemical vapor deposition (ACCVD) method.
2. Experimental procedure
Commercially available MC (TOYO Tanso) was
treated chemically in a mixture of HNO3 and HCl (3:1 byvolume), and is termed as etched MC (EMC) hereafter.
The EMC dispersed in acetone was spin coated onto the
SiO2/Si substrates. Co catalyst (0.2 nm in thickness) was
deposited on them by using a pulsed arc plasma gun, and
SWCNTs growth was carried out on those substrates at
700ºC for 3 min with different partial pressure of Ethanol(EtOH). The grown SWCNTs were characterized by
FESEM, Raman spectroscopy, XPS, and HRTEM.
3. Results and Discussion
Figure 1(a) shows FESEM image of the SWCNTs
grown on EMC at 100sccm EtOH and overlapped
Raman spectra at 90sccm. Thread like structures wereobserved on both SiO2/Si and EMC. Radial breathingmode (RBM), G-band and 2D-band peaks were seen in
Raman spectra after growth, indicating that SWCNTs
were grown successfully on EMC. Figure 1(b) showsthe HRTEM image of the SWCNTs grown at 90sccm
EtOH. FESEM, HRTEM and Raman analysis revealed
that we successfully synthesize SWCNTs and MC 3D
hybrid structure.
This work was supported in part by Private University
Research Branding Project from the MEXT, Japan. We thankProf. Takehiko Hihara at NITech for TEM observation.

[1] Y. Sang et.al. Nano 13 (2018)1850071.
[2] R. Ghosh et al. Chem. Commun. 51(2015) 8974.

Figure 1. SWCNTs grown on EMC (a) FESEM
image of at 90sccm EtOH. (b) HRTEM image of
SWCTs grown at 100sccm EtOH. Overlapped
Raman spectra in (a), and high resolution TEM
image, inset in (b) are of SWCNTs grown at
90sccm EtOH.

Corresponding Author: T. Maruyama
Phone: +81-52-838-2386, Fax: +81-52-832-1172
E-mail: takamaru@meijo-u.ac.jp.

- 81 -

2P-7
Theoretical Design of Thermoelectric Performance of Carbon Nanotube
Thin Films based on Electrical and Thermal Circuit Network Analysis○Junei Kobayashi, Kotaro Fujisaki and Takahiro Yamamoto
Department of Electrical Engineering, Tokyo University of Science, Tokyo 125-8585, JapanThe thermoelectric (TE) devices based on carbon nanotubes (CNTs) thin film are expected to
be flexible and sustainable power resources [1]. It is considered that the TE performance of thethin film depends not only on transport properties of individual CNTs [2] but also on the film
structures such as alignment, density of CNTs and film thickness [3]. However, it has not beenclarified how the macroscopic parameters derived from those structures affect the TE
performance of the film. This means that there currently exist no guidelines to enhance the TE
performance by controlling the macroscopic parameters. Our aim is to establish the guidelines
through computational approach.
In the present study, we focus on the dependence of (i) film thickness and (ii) alignment of
CNTs. We estimated electrical conductivity 𝜎𝜎 , Seebeck coefficient 𝑆𝑆 and Power Factor
𝑃𝑃𝑃𝑃 ≡ 𝜎𝜎𝑆𝑆 2 solving both large-scale electrical and thermal circuit equations for CNT networkmodels (Figs. 1 and 2). The obtained results are summarized as follows. (i) The averaged PF
of CNT films with a fixed area density of CNTs increases with increasing the film thickness.
(ii) The averaged PF of CNT films with a fixed area density of CNTs has the maximum value
at the alignment where the electrical conductivity is maximized, this alignment is intermediate
between perfectly random alignment and well-alignment.

perfectly randomd Fig. 1 Controlled film thickness 𝑑𝑑[1] M. Ohnishi et al., Phys. Rev. B 95, 155405 (2017).

[2] T. Yamamoto et al., J. Phys. Soc. Jpn. 87, 114710 (2018).
[3] M. Tsukuda et al., Appl. Phys. Express 12, 055006 (2019).
Corresponding Author: Takahiro Yamamoto
Tel & Fax +81-3-5876-1492

E-mail: takahiro@rs.tus.ac.jp- 82 -

well-alignment

Fig. 2 Controlled alignment

2P-8
Evaluation of Thermal Transport in a Single-walled Carbon Nanotube Filmby Ionic-liquid Gating○Kan Ueji1, Yuya Matsuoka1, Takashi Yagi2, Kengo Fukuhara1, Yota Ichinose1, Akari
Yoshida1, Yohei Yomogida1, Kazuhiro Yanagi1
12Department of Physics, Tokyo Metropolitan University, Hachioji, Tokyo 192-0397, Japan
National Metrology Institute of Japan, National Institute of Advanced Industrial Scienceand Technology, Tsukuba, Ibaraki,305-8563, Japan

A single-walled carbon nanotube (SWCNT), in which both holes and electrons can flow, is
one of the most promising candidates for flexible thermoelectric generators because of thevan-Hove singularity that originates from the quasi one-dimensional characteristic. The
dimensionless thermoelectric figure of merit (ZT) is given as ZT = σS2T/κ, where σ, S, T, and κ
are the electric conductivity, Seebeck coefficient, absolute temperature, and thermal
conductivity, respectively. A Fermi level of the SWCNT film needs to shift near the van-Hove
singularity level by doping so that the power factor (σS2) is maximized in both puresemiconducting and metallic SWCNT.1 On the other hand, the measurement of κ after
changing the doping level systematically is difficult, indicating that the Fermi level
dependence of κ is indefinite. However, shifting the Fermi level of the SWCNT film results incharge carriers (hole or electron) being placed in the valence or conduction band, which may
affect κ because the charge carriers can interact with acoustic phonons. In fact, Fang et alcalculated that the mobility of acoustic phonons in a graphene nanoribbon vary depending onwhether or not the Fermi level is located in the band.2 To maximize ZT, evaluating not only
the power factor but also κ as a function of the Fermi level is important. Accordingly, we havedeveloped an equipment to simultaneously measure the σ and κ of SWCNT by means of aunique time-domain thermoreflectance method (TDTR) for Au, which is used as a stableelectrode and thermal transducer. We attempt to clarify the κ of SWCNT dependent on the
Fermi level.
Molybdenum (adhesion layer) and gold electrodes were
deposited onto a quartz glass substrate. The
semiconducting SWCNT film with a polycarbonate
membrane was transferred to the substrate, and chloroform
was used to rinse the membrane away, thus resulting in theadherence of the SWCNT film to the measurement
substrate. The sample was annealed at 473 K in vacuo for 2
hours to remove organic impurities. The κ of SWCNT
tuned by the Fermi level was measured by TDTR under Fig. 1 TDTR signals for gold
vacuo. We have a successful TDTR measurement for Au electrode when gate voltage (Vg)change.
during ionic liquid gating as shown in Fig.1. Both thelock-in phase signals are almost same, indicating that the gate voltage range between 0 and−2.5 V have less of an impact on Au. Therefore, it has become possible to measure the κ of
SWCNT film tuning at the Fermi level. In this presentation, we will discuss the variation ofthermophysical properties in the SWCNT film by ionic-liquid gating system.
[1] Y. Ichinose et al., Nano Lett., 19, 7370 (2019) [2] T. Fang et al., Phys. Rev. B, 78, 205403 (2008)
Corresponding Author: K. Ueji and K. Yanagi. Tel: +81-42-677-2494 (Ext. 3253), Fax: +81-42-677-2483,
E-mail: kueji@tmu.ac.jp, yanagi-kazuhiro@tmu.ac.jp- 83 -

2P-9
Thermal stability of single-chirality-enriched carbon nanotube thin films○Akira Takakura1, Taishi Nishihara1, Kazunari Matsuda1, Takeshi Tanaka2,
Hiromichi Kataura2, and Yuhei Miyauchi1
12Institute of Advanced Energy, Kyoto University, Uji, Kyoto 611-0011, Japan.
Nanomaterials Research Institute, AIST, Tsukuba, Ibaraki 305-8565, Japan.

Single-walled carbon nanotubes (SWNTs) have been considered as promising materials forvarious applications utilizing their superior physical properties including high thermal
stability [1] and strength-to-weight ratio [2]. Moreover, recent finding of narrow-band thermalradiation in individual SWNTs relying on excitonic effect has suggested their potential
application as a wavelength selective thermal emitter [1]; a core component inthermophotovoltaic energy harvesting devices [3]. This application requires macroscopic
assemblies of single-chirality enriched SWNTs that can be operated at high temperature (≥700 °C). However, macroscopic aggregation of SWNTs often lowers their excellent intrinsic
properties, and it is still unclear whether the SWNT assemblies are stable enough to be used atelevated temperatures, although individual SWNTs have been confirmed to be stable even at
1700 °C [1].
Here we report the thermal stability of single-chirality-enriched SWNT thin films onvarious substrates. Single chirality SWNTs were separated by gel chromatography [4], and thefilms composed of the SWNTs were fabricated using vacuum filtration method [5]. The
SWNT films were transferred onto metal grids (for fabricating free-standing membranes) orvarious kinds of substrates including sapphire with different crystal planes and quartz. Typical
thickness of the SWNT films was ~100 nm as confirmed via the observation using thescanning electron microscope. The SWNT films were heated up in argon gas flow conditions,and their stabilities were studied using optical techniques such as Raman scattering,absorption and photoluminescence (PL) spectroscopy.
Raman spectroscopy showed that D-mode feature, which is an indicative of the defectdensity, decreased with increasing temperature, in contrast to almost no changes in G-modefeature and optical absorption. The D-mode signals disappeared in the SWNT film after thethermal treatment at 700 °C, irrespective of substrates; this result suggests that the thermal
treatment substantially heals the defects in SWNTs. Enhancement of PL intensities of the
SWNT films, which is also sensitive to the defect density, were also observed. We found thatthe (6,5) enriched SWNT films on the C-plane sapphire were decomposed after the thermal
treatment at 900 °C, in striking contrast to a little decomposition on A-, R-plane sapphire andquartz substrates. This result clearly shows that thermal stability of SWNT films depends on
the kinds of substrate surface. We will discuss the possible mechanism of the substratedependence and the thermal stability of SWNT films with various chiralities to develop ageneral design principle of SWNT thin film devices operating at high temperatures.
[1] T. Nishihara, A. Takakura, Y. Miyauchi, and K. Itami, Nat. Commun. 9, 3144 (2018).
[2] A. Takakura et al. Nat. Commun. 10, 3040 (2019).
[3] E. Rephaeli and S. Fan, Opt. Express 17, 15145 (2009).
[4] Y. Yomogida et al. Nat. Commun. 7, 12056 (2016).
[5] X. He et al. Nat. Nanotechnol. 11, 633 (2016).
Corresponding Author: Y. Miyauchi
Tel: +81-774-38-3463, E-mail: miyauchi@iae.kyoto-u.ac.jp- 84 -

2P-10Relationships between Seebeck coefficient and Conduction Directions
in Aligned Semiconducting Single-wall Carbon Nanotube Films○Kengo Fukuhara1, Yota Ichinose1, Kanako Horiuchi 1, Akari Yoshida 1, Yohei Yomogida 1,
Weilu Gao 2, Natsumi Komatsu 2, Junichiro Kono 2, Kazuhiro Yanagi 1
1

2

Department of Physics, Tokyo Metropolitan University, Tokyo 192-0397, Japan
Department of Electrical and Computer Engineering, Rice University, Texas 77005, USA

Single-wall carbon nanotubes (SWCNTs) are one-dimensional materials with sharp van
Hove singularities. As proposed by Hicks and Dresselhaus, one-dimensional materials havepotential to exhibit superior thermoelectric performance [1], and then their thermoelectric
properties attract a lot of interest. Since SWCNTs have quite an-isotropic structure, previously,
we investigated thermoelectric properties depending on
conduction directions, such as parallel or perpendicular adirections to the nanotube axis, using aligned SWCNT
thin films [2]. We observed an-isotropic character inelectrical conductivity, but completely isotropic characterin Seebeck coefficient regardless of the conduction
directions. Such isotropic character in Seebeck coefficient
will reflect that the conduction mechanism in the parallel
direction is similar hopping conduction to theperpendicular direction. However, if the mechanisms aredifferent between the two directions, Seebeck coefficient
may also exhibit an-isotropic character. To check thishypothesis, in this study, we investigated electricalbconductivity and Seebeck coefficients of aligned metallic
and semiconducting SWCNT films. We fabricatedlarge-area aligned SWCNT films using the slow filtration
method [3]. Then we measured electrical conductivity andSeebeck coefficient as a function of Fermi level in paralleland perpendicular directions. Figure 1 shows therelationships between Seebeck coefficient and electricalconductivity in parallel and perpendicular directions inmetallic and semiconducting SWCNTs. We found that in
the case of semiconducting SWCNTs, Seebeck coefficient
showed something different line-shapes as shown using Figure 1. The correlation
dash lines in small electrical conductivity region. This between Seebeck coefficientresult may suggest an-isotropic character in Seebeck and electrical conductivity(a) is the metallic and (b) is thecoefficient in aligned semiconducting SWCNT films.
semiconducting sample.
Reference: [1] Hicks & Dresselhaus, PRB 47, 16631(1993) [2] Fukuhara et al., APL 113, 243105 (2018) [3] He et al., Nat. Nanotechnol. 11, 1(2016)
Corresponding Author: K. Yanagi, Tel: +81-42-677-2494, E-mail: yanagi-kazuhiro@tmu.ac.jp- 85 -

2P-11
Macroscopic four probe thermal and thermoelectric measurement ofcarbon nanotube fibers
Akito Sato 1, Kento Adachi 1, ○Takashi Kodama 1
1

Department of Mechanical Engineering,The University of Tokyo, Tokyo 113-8656, Japan

Carbon nanotubes (CNT) are one of most famous carbon nanomaterials and attract theinterest in thermal management society for future thermal engineering application due to its
excellent thermal and thermoelectric properties at nanoscale. Since most industrial
applications require the bulk form, the CNTs must be made macroscopic structure such as thethin film and the CNT fibers [1] fabricated by various spinning method has been extensively
investigated for the future application. However, it has been reported that the bulk propertiesof CNTs are varied depending on the material structure, and in particular, the structuraldependent thermal and thermoelectric properties of CNTs has not been clarified so far due tolack of a simple and accurate measurement technique.
The suspended microfabricated device is generally utilized to estimate the thermal
conductivity and thermoelectrical properties of nanomaterials to suppress and to define theheat loss through the measurement system [2], and a four probe thermal conduction
measurement method has been recently reported to separate the thermal boundary
conductance between sample and measurement structure from the measured thermal
conductance, which becomes a cause of serious measurement error [3]. However, theappropriate device design is usually required depending on the material of interest and thedevice microfabrication cost is not neglectable for the simple evaluation of the thermal
conduction properties. Furthermore, thermal conductivity measurement with themicrofabricated device is not suitable for the measurement of macroscopic materials in termsof the measurement sensitivity.
Thus, we develop a simple thermal and thermoelectric measurement technique formacroscale fiber materials based on the nanoscale four probe thermal conduction
measurement method. The measurement technique does not require the complicated device
microfabrication process and the measurement system is composed of the suspended fourbulk platinum wires with the samples at the center of the wires manipulated with a standard
bonding machine. In the presentation, we demonstrate the simultaneous measurement ofelectrical conductivity, thermal conductivity, and the thermoelectric power of CNT fibers
fabricated with a wet spinning method and report the details of the measurement technique.
[1] K. Mukai et al. Appl. Phys. Express 9, 055101(2016).
[2] T. Kodama et al. Nat. Mater. 16, 892 (2017).
[3] J. Kim et al. Rev. Sci. Instrum. 86, 044901(2015).
Corresponding Author: T. Kodama
Tel: +81-3-5841-2744, Fax: +81-3-5841-8091,
E-mail: kodama@photon.t.u-tokyo.ac.jp
Fig.1 Photograph of the macroscopic four probe
thermal measurement device- 86 -

2P-12
Bubble induced electron beam damage on graphene liquid cells during
TEM observation
Sota Hirokawa1, Hideaki Teshima1,2, Pablo Solis Fernandez3, Hiroki Ago3, Yoko Tomo4,
Qin-Yi Li1,2, Koji Takahashi 1,2
1

Department of Aeronautics and Astronautics, Kyushu University, 744 Motooka, Nishi-ku,
Fukuoka 819-0395, Japan
2
International Institute for Carbon-Neutral Energy Research (WPI-I2CNER), Kyushu
University, 744 Motooka, Nishi-ku, Fukuoka 819-0395, Japan3
Global Innovation Center, Kyushu University, 6-1 Kasuga-koen, Kasuga-city, Fukuoka
816-8580, Japan
4
Department of Mechanical Engineering, Kyushu University, 744 Motooka, Nishi-ku,
Fukuoka 819-0395, Japan
Graphene liquid cells (GLCs) allows highest possible spatial resolution for liquid phasetransmission electron microscopy (TEM)[1]. However, long time observation using GLCs islimited owing to the inevitable electron irradiation damage[2], [3]. Here, we investigate theoccurrence of damage in the GLC wrapping water pockets under several electron beam
conditions. Comparison of our observation proves that TEM with lower electron dose rate canreduce the damage possibility. Interestingly, during the observation of water pockets
encapsulating no-bubbles, we never found the damage of GLC even with highest electron
dose rate TEM. This fact indicates that electron beam induced damage in graphene depends
on not only the electron dose rate but also whether there is bubbles in the GLC.
In addition, we use GLCs to study nanoscale dynamics that is induced by controllable
damage in graphene. We observed air molecule leakage from bubble to water and unexpected
directional nucleation of new bubbles, which is beyond the explanation of conventional
diffusion theory.
[1]
[2]
[3]

J. M. Yuk et al., Science, 336, 61–64, (2012).
D. Shin et al., Nat. Commun., 6, 1–6, (2015).
L. Wang et al., Microsc. Microanal., 23, 866–867, (2017).

Corresponding Author: K. Takahashi
Tel: +81-92-802-3015
E-mail: takahashi@aero.kyushu-u.ac.jp

Fig.1. TEM image of a water pocket andencapsulated bubble (left). After GLC got
damage, water and the bubble disappeared(right). Scale bar is 50 nm.

Fig.2. Relationship between GLC damage
occurrences and size of water pockets andcorresponding bubbles.

- 87 -

2P-13
Strain-Induced Enhancement of Thermoelectric Power Factor of Graphene○Kohei Suzuki1, Kenji Sasaoka2 and Takahiro Yamamoto1,2
1

Department of Electrical Engineering, Tokyo University of Science, Tokyo 125-8585, Japan
2
Water Frontier Science & Technology Research Center, Tokyo University of Science,
Katsushika-Ku, 125-8585, Japan

Thermoelectric conversion is a key technology for sensor batteries for Internet of Things (IoT).
Graphene is a potential candidate for flexible and sustainable thermoelectric materials. In fact,
a previous experimental study reported the large power factor (PF=𝑆𝑆𝑆𝑆 2 𝜎𝜎𝜎𝜎) of graphene films[1],where 𝜎𝜎𝜎𝜎 is electrical conductivity and 𝑆𝑆𝑆𝑆 is Seebeck coefficient. This large power factor
originates from the high electrical conductivity, but the Seebeck coefficient is not large enough.
In order to enhance the PF of graphene, we need to increase the Seebeck coefficient byintroducing new technology.
As a new technology, we introduce the application of strain to the graphene, which has
attracted much attention as a band-gap engineering[2]. In this study, we performed numericalsimulation based on the non-equilibrium Green’s function method combined with the tightbinding method. First, we calculated the chemical potential dependence of the power factor ofa graphene under the local strain along the armchair direction at 300 K, which can beexperimentally induced by shrinking the graphene films[3]. The obtained power factor has thepeak structure at a certain chemical potential value, irrespective of the local strain. Fixing thechemical potential to this value, we estimate the strain dependence of the electrical conductance,
the Seebeck coefficient and the power factor. The obtained results show that the Seebeckcoefficient becomes larger with increasing the strain whereas the electrical conductancedecreases. In addition, we clarified that the power factor is maximized at about 1 % strain. The
maximum value becomes 1.4 times larger than the power factor of pristine graphene.
[1] K. Kanahashi, et al. npj 2D Materials and Applications, 44, 3 (2019).
[2] S. Souma, et al., Phys. Lett. 104, 213505 (2014)[3] H. Shioya et al., Nano Lett. 14, 1158 (2014).
Corresponding Author: Takahiro Yamamoto
Tel & Fax: +81-03-5876-1486,
E-mail: takahiro@rs.tus.ac.jp- 88 -

2P-14Spin-Filter Effect of Zigzag Graphene Nanoribbons with Edge Defects○Naoya Abe1, Kenji Sasaoka2 and Takahiro Yamamoto1,2,3
1

Department of Electrical Engineering, Tokyo University of Science, Tokyo 125-8585, Japan
2
Water Frontier Science & Technology Center, Tokyo University of Science, Japan3
Department of Liberal Arts, Tokyo University of Science, Tokyo 125-8585, Japan

Spintronics is expected to one of new electronics for next generation, which utilizes not
only charge degrees of freedom but also spin degrees of freedom. Many spintronic devices havebeen proposed, e.g., a new device switching between up- and down-spin channels by thechemical potential [1]. This switching device performance can be evaluated by spin filter
efficiency. One of the potential candidates for this switching device’s materials is a hydrogenterminated zigzag graphene nanoribbons (H-ZGNRs). Since the H-ZGNR is an atomic layermaterial, the gate voltage can be applied to the H-ZGNRs more efficiently than bulk materials.
In addition, the H-ZGNRs are known to have edge magnetization [2] and their long spin
relaxation time and long spin diffusion length are also advantage for the spintronics devices [3].
However, performance of spin filter effect under edge defects remains to be resolved thus far.
In this work, the spin-filter effect with edge defects of H-ZGNRs of about 10 nm in length,
which is shorter than the spin diffusion length [3], is computationally examined using the density
functional theory (DFT) method combined with the non-equilibrium Green's function (NEGF)
technique. The exchange-correlation potential in the DFT calculation is treated as the local spin
density approximation (LSDA). Moreover, we assume that the ground state of H-ZGNR isferromagnetic. For this case, we calculate the electrical conductance of an H-ZGNR
with/without edge defects. From our simulation results, we found that the spin filter efficiency
exceeds 99% at characteristic chemical potential in the presence of the edge defects. Thisoriginates from Fano resonance originating from the defect level lying in the continuum
electronic state of an H-ZGNR.
[1] K. Yabusaki et al., Jpn.J.Appl.Phy. 58,045001 (2019).
[2] Y. W. Son et al., Natute 444, 347 (2006).
[3] N.Tombros et al., Nature 448, 571 (2007).
Corresponding Author: Takahiro Yamamoto
Tel&Fax: +81-3-5876-1492
E-mail: takahiro@rs.tus.ac.jp- 89 -

2P-15
Anomalous electroluminescencefrom WS2/WSe2 in-plane heterostructures○Naoki Wada1, Jiang Pu2, Tomoyuki Yamada2, Wenjin Zhang3, Zheng Liu4, Yusuke
Nakanishi1, Yutaka Maniwa1, Kazunari Matsuda3, Yuhei Miyauchi3, Taishi Takenobu2,
Yasumitsu Miyata1
1

Department of Physics, Tokyo Metropolitan University, Hachioji 192-0397, Japan2
Department of Applied Physics, Nagoya University, Nagoya 464-8603, Japan
3
Institute of Advanced Energy, Kyoto University, Uji, 611-0011, Japan
4
Inorganic Functional Materials Research Institute, AIST, Nagoya, 463-8560, Japan
Heterostructures of transition metal dichalcogenides (TMDCs) are an attractive system
to realize high-performance devices such as light-emitting diodes and tunnel field-effecttransistors. To investigate their electronic properties and device performance, we havedeveloped growth processes of various in-plane heterostructures based on TMDC
monolayers. In our previous studies, we have demonstrated the electric double layer lightemitting diodes (EDLEDs) using these in-plane heterostructures [1-3]. In particular, werecently found that some samples show unique electroluminescence (EL) peaks, whichhave never been observed for photoluminescence spectra. However, the origin of theseEL peaks is still unknown. In this study, we have investigated the spatially-resolved EL
spectra of WS2/WSe2 in-plane heterostructures. The samples were grown by chemical
vapor deposition (Fig.1a), and then EDLEDs were fabricated (Fig.1b). The device shows
linear EL along the heterointerface by applying bias voltage (Fig. 1c). Interestingly,
multiple EL peak components can be observed at a specific position along the interface
as shown in Fig.1d. This suggests that the interface EL could be used to probe interfacederived electronic states and optical transitions. In this presentation, we will discuss about
the detail of voltage- and site-dependent EL properties.

Fig.1 (a) Illustration of growth model of WS2/WSe2 in-plane heterostructures. (b) Optical and (c) EL
images of WS2/WSe2-based EDLED device. (d) EL spectrum obtained at the interface.
[1] J. Pu et al., Adv. Mater. , 29, 1606918 (2017). [2] Y. Takaguchi et al., 56th FNTG symposium.
[3] N. Wada et al., 57th FNTG symposium.
Corresponding Author: Yasumitsu Miyata, Tel: 042-677-2508, E-mail: ymiyata@tmu.ac.jp- 90 -

2P-16
Absolute and relative intensity of the C60 IR absorption○Tomonari Wakabayashi1, Takamasa Momose2, Mario E. Fajardo3
Department of Chemistry, Kindai University, Higashi-Osaka, Osaka 577-8502, Japan
Department of Chemistry and Department of Physics and Astronomy, The University of
British Columbia, Vancouver, British Columbia 6VT 1Z1, Canada
3
Munitions Directorate, US Air Force Research Laboratory AFRL/RWME, Eglin AFB,
Florida 32542-5910, USA
1
2

The detection of C60 and C70 in space by the infrared (IR) emission spectra of planetarynebulae has rekindled interest in absolute band strengths of dipole-allowed infrared (IR)transitions of fullerenes for the estimation of their abundances [1,2]. Four IR-active vibrationalmodes of C60 are known to be key probes for the carbon molecule of high symmetry [3]. They
are triply degenerate modes of T1u symmetry and the behaviors are tricky when the icosahedral
symmetry of Ih in 12C60 is lowered by isotopic substitutions of 12C nuclei by heavier 13C isotopes.
We studied in this work effects of isotopic substitutions on vibrational spectra by matrix
isolation spectroscopy of C60 in cryogenic solid parahydrogen (pH2), orthodeuterium (oD2), andneon (Ne) matrix hosts using isotopically manipulated C60 samples and by molecular orbital(MO) calculations at B3LYP/6-31G(d) level of density functional theory (DFT) for the mostimportant 328 distinct isotopomers of 13Cn12C60-n of n = 0, 1, 2, and 3 [4].
Three-fold degeneracy of the T1u mode islifted upon 13C-isotopic substitution into three
distinct modes of different frequencies. The
vibrational frequencies are lowered and the IR
absorption intensities are decreased. IR-silent
modes in Ih symmetry are activated for the IR
absorption for vibrational modes of nearby
frequencies to the T1u modes. With increasing
13
C abundance, contributions from isotopically
substituted species, 13Cn12C60-n of n ≥ 1, to the
IR intensity of the other modes than T1u
increase. Nevertheless, the sum intensity of the
split T1u modes and the IR-activated modes ofnearby frequencies remains constant (Fig. 1).
The relative intensities observed by matrix
isolation spectroscopy are well reproduced by
the calculations. For a conclusion, we suggest Fig. 1. Calculated band strengths of the four IR-active
a set of IR band strengths for the four IR-activemodes of C60 vs 13C abundance: T1u(1) at 18.9 μm,
T1u modes of fullerene C60 based on the present
T1u(2) at 17.4 μm, T1u(3) at 8.5 μm, and T1u(4) at
7.0 μm. Solid lines indicate IR absorption intensity
DFT-MO calculation, e.g., S = 27.1 km/mol for-1of
328 isotopomers of 13Cn12C60-n up to n = 3, while
T1u(3) at 1185 cm (8.5 μm). For the others,
dotted lines include contributions from highly
see Fig. 1.
substituted isotopomers of n ≥ 4.
[1] J. Cami, J. Bernard-Salas, E. Peeters, and S. E. Malek, Science 329, 1180 (2010).
[2] M. Otsuka, F. Kemper, J Cami, E. Peeters, and J. Bernard-Salas, Mon. Not. R. Astron. Soc. 437, 2577 (2014).
[3] W. Krätschmer, K. Fostiropoulos, and D. R. Huffman, Chem. Phys. Lett. 170, 167 (1990).
[4] T. Wakabayashi, T. Momose, and M. E. Fajardo, J. Chem. Phys. 151, 234301 (2019).
Corresponding Author: T. Wakabayashi, Tel: +81-6-4307-3408, E-mail: wakaba@chem.kindai.ac.jp- 91 -

2P-17
A one-step direct oxidation of alkoxy to ketone: oxidation of alkoxy
indano[60]fullerenes to [60]fullerene-fused ketones via weak copper oxidant○Yue Ma 1, Hao-Sheng Lin 2, Yun Yu1 , Shigeo Maruyama2, Il Jeon2, Yutaka Matsuo 1,2
1

Hefei National Laboratory for Physical Sciences at Microscale, University of Science andTechnology of China, 96 Jin-zhai Road, Hefei, Anhui 230026, China
2
Department of Mechanical Engineering, School of Engineering, The University of Tokyo,
Bunkyo-ku, Tokyo 113-8656, Japan

Considerable endeavors have been devoted to selective oxidation of alcohols to ketones in
the field of organic chemistry. However, all protocols turn into ineffective once alcohols areprotected/functionalized by alkyl group that forming the alkoxy group. Consequently, theone-step oxidation of alkoxy to ketone has never been unveiled and still remains greatchallenges, especially by using weak oxidants. Recently, carbonyl [60]fullerene and its
derivatives have attracted intensive attentions due to their impressively potential applications
in photovoltaics. Among these carbonyl [60]fullerene derivatives, the fullerene-fused ketone
has more potential for photovoltaics owing to its unique full-carbon-five-membered ring
structure, and the synthetic building block that the ketone moiety renders.
In this work we realized the one-step direct oxidation of alkoxy indano[60]fullerenes to[60]fullerene-fused ketones through weak oxidant, CuBr2, in moderate yields with anexcellent functional group tolerance. The products were unambiguously characterized by
NMR spectroscopy, MALDI-TOF mass spectrometry. The reaction mechanism wasthoroughly studied via analyzing the intermediate, isotopy effect and EPR measurement.
Besides, the reaction scope was enlarged via the optimized reaction condition.
Figure 1. The concept of CuBr2-promoted one-step oxidation of alkoxy indano[60]fullerenes tofullerene-fused ketones.
.

[1] Lin, H-S. et al. Chem. Mater. 2019, 31, 8432−8439
Corresponding Author: Y. Matsuo
Tel: +81-3-5841-0978, E-mail: matsuo@photon.t.u-tokyo.ac.jp- 92 -

2P-18
ESR study of La and Y hetero-dimetallofullerene anions○Moeno Maejima, Koichi Kikuchi, Yohji Achiba, Takeshi Kodama
Department of Chemistry, Tokyo Metropolitan University, Tokyo 192-0397, Japan
Dimetallofullerene anions [M2@Cn]- (M = Y and La) (n = 78, 80) have an electron on theinternal M2 dimmer, which is mainly composed of s and d orbitals [1]. ESR is a powerful tool
to reveal the nature of the dimer orbital via hyperfine coupling constants. In this study, we
synthesized and isolated hetero-dimetallofullerene anions, [LaY@Cn]-, to elucidate thecharacter of the hetero-dimer orbital by ESR.
Soot containing metallofullerenes was produced by DC arc discharge under He atmosphere.
The produced soot was extracted by a mixture of acetone and triethylamine. The separation
was performed by HPLC. Sample isolation was confirmed by LD-TOF-MS and the cage
structure was identified by UV-Vis-NIR absorption. Electronic structure of [LaY@Cn]- wasinvestigated by X-band ESR.
Fig. 1 shows the ESR spectrum of [LaY@C78]-. Although the three peaks due to a small
amount of not separated [Y2@C78]- was observed, the other 16 peaks were assigned to anelectron spin on the internal La-Y dimmer of [LaY@C78]-, S=1/2, coupled with nuclear spinsof 139La(I=7/2) and 89Y(I=1/2). From the spectrum simulation, the isotropic g factor (giso) andthe hyperfine coupling constants (Aiso) for La and Y were obtained and listed in Table 1 withthe results of [Y2@C78]- and [La2@C78]- [2, 3].
Aiso is proportional to the spin density on the nucleus, then it represents a degree of thes-orbital contribution. Aiso for Y of [LaY@C78]- is larger than that of [Y2@C78]- while Aiso for
La is smaller than that of [La2@C78]-. Therefore, it was suggested that the density of an
unpaired electron on Y is larger than that of La in [LaY@C78]-. This result is reasonablebecause the dimmer orbital composed of 4d, 5s-orbital of Y and 5d, 6s-orbitals of La and theenergy of 5s-orbital of Y is lower than that of 6s-orbital of La.
In the symposium, the results of low temperature ESR for [LaY@C78]- and [LaY@C80]will be also discussed.

Table 1 ESR parameters
giso
Aiso/MHz[LaY@C78]-[Y2@C78]-[La2@C78]-

1.951

1.985

1.961

170

827

668 (La)
235 (Y)Fig.1 ESR spectrum of [LaY@C78][1] A. Velloth et al. J. Phys. Chem. C. 121, 18169 (2017).
[2] N. Nakatori et al. The 50th Fullerenes-Nanotubes-Graphene General Symposium 44 (2016).
[3] S. Nishimoto et al. The 52nd Fullerenes-Nanotubes-Graphene General Symposium 129 (2017).
Corresponding Author: Takeshi Kodama
Tel: +81-42-677-2530, Fax: +81-42-677-2525, E-mail: kodama-takeshi@tmu.ac.jp- 93 -

2P-19ESR Study of two isomers of [Sc2C80]-: [Sc2C80(1)]- and [Sc2C80(2)]○Shun Yoshida1, Ko Furukawa2, Koichi Kikuchi1, Yohji Achiba1, Takeshi Kodama1
12

Department of Chemistry, Tokyo Metropolitan University, Tokyo 192-0397, Japan
Center for Coordination of Research Facilities, Niigata University, Niigata 950-2181, Japan

In the previous symposium, we reported the isolation of two isomers of [Sc2C80]-:[Sc2C80(1)]- and [Sc2C80(2)]- [1]. Moreover, X-band ESR spectra of them at room temperature
were measured [2]. Both ESR spectra for [Sc2C80(1)]- and [Sc2C80(2)]- showed the isotropic
patterns due to the fast motion in solution, and were essentially consisted of 64 peaks,
respectively (some peaks were overlapped). The spectral simulation reproduced well the
spectra, and the obtained isotropic hyperfine coupling constants (Aiso), which come from theinteraction between an unpaired spin and nuclear spin of Sc (I=7/2), were very large:
Aiso(1)=497.5 MHz, Aiso(2)=464.9 MHz. Therefore, it was concluded that an unpaired spin is
located on the encaged Sc dimer because Aiso is proportional to spin density on the metal
nucleus. In this study, to investigate the spin state of two isomers of [Sc2C80]- more in detail,we measured X-band cw-ESR spectra and Q-band ESEFS (Electron-Spin-Echo detected
Field-Sweep) spectra at low temperature.
Fig. 1 is the X-band cw-ESR spectrum of [Sc2C80 (1)]- and showed very complex andanisotropic pattern due to the random orientation of [Sc2C80 (1)]- fixed in frozen solution. Fig.
2 is Q-band ESEFS spectrum of [Sc2C80 (1)]-. Because the microwave frequency for Q-bandmeasurement is about 4 times larger than that for X-band, Zeeman interaction is dominant
over hyperfine interaction, and the latter contributes as perturbation. Therefore the spectralfeature for Q-band is rather simple compared with X-band. Both two spectra were simulatedby the same set of parameters.
In the symposium, the assignments of the peaks of these spectra with the results of[Sc2C80(2)]- will be discussed.

Fig. 1 X-band cw-ESR spectrum of [Sc2C80(1)]- (4 K)

Fig. 2 Q-band ESEFS spectrum of [Sc2C80(1)]- (10 K)[1] S.Yoshida, et al. The 55th Fullerenes-Nanotubes-Graphene General Symposium 126 (2018).
[2] S.Yoshida, et al. The 56th Fullerenes-Nanotubes-Graphene General Symposium 59 (2019).
Corresponding Author: Takeshi Kodama
Tel: +81-42-677-2530, Fax: +81-3-42-677-2525
E-mail: kodama-takeshi@tmu.ac.jp- 94 -

2P-20
Doped-site structure dependent energy shifts of photoluminescencefrom locally functionalized single-walled carbon nanotubes
in organic solvent environments○Tomohiro Shiraki1,2, Yoshiaki Niidome1, Tsuyohiko Fujigaya1,2,3
1

Department of Applied Chemistry, Kyushu University, Fukuoka 819-0395, Japan
2
WPI-I2CNER, Kyushu University, Fukuoka 819-0395, Japan
3
CMS, Kyushu University, Fukuoka 819-0395, Japan

E

11

2

* / meVSingle-walled carbon nanotubes (SWNTs) show near infrared photoluminescence (PL)whose energy is sensitively changed by their microenvironments composed of surfactants andsolvents.[1] The PL properties have been found to be enhanced by defect doping that isachieved by local chemical functionalization of SWNTs. As one example of synthetic
methods of the locally functionalized SWNTs (lf-SWNTs), diazonium chemistry using
aryldiazonium salts was reported to produce sp3 carbon defects in the sp2 carbon network of
the SWNTs via the aryl group functionalization.[2] The lf-SWNTs emit E11* PL that has
narrower band-gap energies with higher quantum yields compared to E11 PL of pristine
SWNTs. In addition, E11* PL energies are modulated depending on the chemical structures ofthe functionalized aryl groups at the doped sites. Very recently, we have reported that E11* PLshowed larger energy shifts than E11 PL when organic solvents were injected to the aqueous
lf-SWNTs solubilized by surfactant micelles.[3] This result shows that the doped sites havehigh sensitivity to the microenviroments, and the unique properties are expected to bemodulated depending on the difference in chemical structures of the doped sites of lf-SWNTs.
In this study, we examined microenvironment
5effects of the lf-SWNTs having different doped sites
structures: bis-aryl functionalized lf-SWNTs that0show E112* PL appearing longer wavelength regions
than typical E11* PL [4] and oxygen(O)-doped-5
lf-SWNTs that have defects with ether or epoxide
structures.[5] Fig. 1 shows energy shifts of E112*-10
PL from bis-aryl functionalized lf-SWNTs (E112*)
as a function of a solvent polarity parameter of f(ε)-15
− f(η2). The E112* showed larger energy shifts
according to the increase in the values of f(ε) − f(η2)-20with a liner correlation. By comparison of the
0
0.1
0.2
0.3
0.4
2
f( ) - f( )lf-SWNTs with different structures including
O-doped ones, the shifting manner was found to Fig.1 Plots of ΔE112* as a function of f(ε)
2change with strong dependence on the chemical − f(η ) for bis-aryl functionalized lf-SWNTs
that were treated by injection of organic
structures of doped sites.
solvents.

[1] Y. Ohno et al. Phys. Status Solidi B. 244, 4002 (2007). [2] Y. Wang et al. Nat. Chem. 5, 840 (2013). [3] T.
Shiraki et al. Chem. Commun. 55, 3662 (2019). [4] T. Shiraki et al. Sci. Rep. 6, 28393 (2016). [5] Y. Miyauchi
et al. Nat. Photon., 7, 715 (2013).
Corresponding Author: T. Fujigaya
Tel: +81-92-802-2842, Fax: +81-92-802-2842
E-mail: fujigaya.tsuyohiko.948@m.kyushu-u.ac.jp- 95 -

2P-21
Electrical detection of X-ray by using coplanar CNT thin-film electrodes
on PEN substrate○Hiroyuki Matsuda1, Satoru Suzuki1, Takahiro ishikawa2, Teruaki Konishi2,
Tsuyoshi Hamano2, Yutaka Ohno3,4, Toshio Hirao2, Satoshi Ishii1
Department of Physics, Tokyo Denki University, Saitama 350-0394, Japan
National Institute for Radiological Sciences, National Institutes for Quantum andRadiological Science and Technology, Chiba 263-8555, Japan3
Department of Electronics, Nagoya University, Nagoya 464-8602, Japan
4
Institute of Materials and Systems for Sustainability, Nagoya University, Nagoya 464-8601,
Japan
1

2

Radiation exposure to the eye lens has been a problem for a curer in the radiation therapy.
Then, the transparent real-time dosimeter is required to measure the eye dose without
disturbing their eyesight. In order to develop the transparent detector, transparency isnecessary not only for the substrate but also for the electrode.
Carbon nanotube is known to have transparency along with
1 mmradiation tolerance [1]. In this study, we have fabricated thePEN sheet
125 mcoplanar CNT thin-film electrodes on the PEN sheet andFig.1 Device structure.
conducted the direct electrical detection of X-ray using these.
Figure 1 shows the schematic structure of the device, where
X-ray onmGy/secOffthe distance between the CNT thin-film electrodes was 1 mm.
36.10
The electrodes were patterned on the PEN substrate by splay
20.54
coating of the single-walled CNT dispersion in IPA (0.2 wt%)
10.18
using the metal mask. The device was placed inside of the
5.57
2.36
stainless chamber under a vacuum of 1.0×10-2 Pa. X-ray with
1.18
an effective energy of 83 keV was irradiated to the device fromoutside of the chamber at a bias voltage of 10 V. The current of
the device was measured in real time during turning on and off Fig.2 Time dependence ofthe current.
of the irradiation at each dose rate.
The current was confirmed to respond to the X-ray
irradiation, as shown in Fig. 2. Moreover, the generated current
increased linearly with the dose rate below 10.18 mGy/sec, as
shown in Fig. 2, although it no longer changed linearly above
20.54 mGy/sec. It is thought that the generated current was the@10 V
charges originated from the ionized residual gas inside thechamber, and that it did not reach the saturated region under thebiased voltage. The CNT thin-film electrodes on the PEN sheet
Fig.3 Dose rate dependence
is applicable to the real-time transparent detector.
of the generated current.
This work was supported partially by the joint usage/research program of the Institute of Materials andSystems for Sustainability (IMaSS), Nagoya University.
[1] S. Ishii et al. Physica E. 86, 297 (2017).
Corresponding Author: S. Ishii
Tel: +81-49-296-1926, Fax: +81-496-296-2915,
E-mail: s.ishii@mail.dendai.ac.jp- 96 -

2P-22
Understanding and controlling the pyrolysis of C3H8 for uniform
synthesis of vertically-aligned single-wall carbon nanotubes○Meng-Ju Yang1, Pengfei Chen1, Rei Nakagawa1, Hisashi Sugime1, Hitoshi Mazaki2, Suguru
Noda1,3,*
1

Department of Applied Chemistry, School of Advanced Science and Engineering, Waseda
University, 3-4-1 Okubo, Shinjuku-ku, Tokyo 169-8555, Japan
2
Central Technical Research Laboratory, JXTG Nippon Oil & Energy Corporation, 8
Chidori-cho, Naka-ku, Yokohama, Kanagawa 231-0815, Japan

3

Waseda Research Institute for Science and Engineering, Waseda University, 3-4-1 Okubo,
Shinjuku-ku, Tokyo 169-8555, Japan

Single-wall carbon nanotubes (SWCNTs) havebeen extensively researched, but the low-cost mass
production of high-quality SWCNT is still achallenge. Among others, C2H2 is known as a highly
active carbon feedstock which can growvertically-aligned SWCNTs (VA-SWCNTs) directly
without gas-phase reactions [1]. However, larger
area SWCNT growth is difficult because supplying
C2H2 with high concentration tends to deactivate thecatalysts easily [2]. Therefore, controlling thegas-phase reactions is important for the large area
growth as shown with the combined feed of C2H2
and C2H4 in our previous report [3]. From thisviewpoint, the low-activity carbon feedstocks are
considered to play an important role. Some carbon
species were previously studied [4], however the
possibility of the SWCNT growth with thinner Fe
conditions was overlooked since the catalyst
Fig. 1: (a) Side-view images of the SWCNT
condition was fixed. In this study, by changing Fe forests with different Fe thickness (on Al2Ox/Si
thickness of Fe/Al2Ox/Si samples using our original samples) at 800 °C after 30 min using C3H8 or
combinatorial method [5], the growth of C2H2. (b) Areal mass of the SWCNTs
millimeter-tall VA-SWCNTs is studied using C3H8 corresponding to the samples shown in (a).
as a carbon feedstock. It was found that, compared to C2H2, C3H8 can grow larger amount of
the VA-SWCNTs with thinner Fe (Fig. 1a). With 0.40 nm Fe, the average areal SWCNT yield
at 800 °C for 30 min was 3.4 mg cm-2 with C3H8 whereas it was 1.4 mg cm-2 with C2H2 (Fig.
1b). The analysis of the gas species by gas chromatography indicated that C3H6 which was
generated by the decomposition of C3H8 plays a key role for the SWCNT growth.
[1] H. Sugime et al., Carbon 50, 2953 (2012). [2] K. Hasegawa et al., ACS Nano 5, 975 (2011). [3] T. Sato et al.,Carbon 136, 143 (2018). [4] H. Kimura et al., ACS Nano 7, 3510 (2013). [5] S. Noda et al., Carbon 44, 1414
(2006).

Corresponding Author: S. Noda, Tel: +81-3-5286-2769, E-mail: noda@waseda.jp- 97 -

2P-23Synthesis of boron nitride nanotube by chemical vapor deposition
using new boron source○Tetsuro Sawada1, Hiromu Takahashi1, Tomohiro Sei1, Mayu Asaka1, Toshio Osawa1,
Hisashi Sugime1, Suguru Noda1,2,*
1

The Department of Applied Chemistry, 2Waseda Research Institute for Science and Engineering,
Waseda University, Tokyo 169-8555, Japan.

Boron Nitride Nanotube (BNNT) has high thermal stability, chemical stability, and thermal
conductivity similarly to carbon nanotube (CNT) with electrical insulation and opticaltransparency oppositely to CNT. We may design various new devices by combining them.
Physical vapor deposition (PVD) is known as a production method for high quality BNNT [1].
However impurities such as B-powder and h-BN flakes are included at high contents in the
product, and high production cost stems from the very high temperature and solid source
materials (B or BN powders) used in the PVD processes. Chemical vapor deposition (CVD) isanother production method of BNNT that may enable its mass production at low cost due tothe moderate reaction temperature and gaseous source materials. Ammonia (NH3) is aneffective nitrogen source of low cost [2], however there lack the good boron source of low
cost and low risk. For example, diborane is highly explosive and poisonous while BCl3 etchthe catalyst away. Borazine and ammonia borane are widely used for h-BN atomic layers but
expensive for mass production of BNNTs.
In this work, we report boric acid (H3BO3) as a new boron source of low cost and low risk.
BNNT was synthesized on graphite substrates with sputter-deposited Fe catalyst using a
conventional tubular thermal CVD reactor. BNNT was synthesized at 950 °C for 10 min byfeeding H3BO3 vapor and NH3 Ar carrier gas. The as-grown substrates were analyzed byscanning electron microscope (SEM) and Raman scattering spectroscopy (excitation
wavelength: 633 nm). The color of the graphite substrates turned from gray to white. The
SEM image showed many tube-like structures (Fig. 1), and the Raman spectroscopy showed
peaks at ~ 1370 cm-1 (not shown) originating from h-BN structure [2]. These results showedthat BNNT were synthesized using the new boron source, i.e. H3BO3 vapor.

Fig. 1. SEM image of BNNT produced by CVD using H3BO3 and NH3 sources and Fe/graphite substrate.
[1] K. S. Kim et al., Semicond. Sci. Technol. 32, 013003 (2017).
[2] P. Ahmad et al., RSC Adv. 20, 35116 (2015).
Corresponding Author: S. Noda, Tel: 03-5286-2769, E-mail: noda@waseda.jp- 98 -

2P-24
Sublimation property of a flavin compound which is a surfactant for
carbon nanotube dispersion○Yuichi Kato,1 Kazufumi Kobashi,1 Takeo Yamada,*1 and Kenji Hata1
1

CNT-Application Research Center, National Institute of Advanced Industrial Science andTechnology (AIST), Central 5, 1-1-1 Higashi, Tsukuba 305-8565, Japan

Dispersing to liquid with surfactants has been an important technique to utilize uniqueelectronic property of single-walled carbon nanotubes (SWNTs), especially in the ﬁeld ofelectronics. Surfactants play an important role to strongly adsorb and stabilize to isolated
SWNT. On the other hand, the strongly adsorbed surfactants have problems of removal. An
approach to remove surfactants is a wet process; adsorption stability control has been studied.
The other possible approach for removing is a dry process of gasification. In this presentation,
we
show
the
sublimabilityofaflavincompound,[1]
10-dodecyl-7,8-dimethyl-10H-benzo[g]pteridine-2,4-dione (dmC12, Fig. 1a), which is asurfactant for carbon nanotube dispersion (Fig. 1b) and chirality separation.
We heated dmC12 in a flask to 240-260°C with a mantle heater under low pressure
conditions (0.65-3×103Pa) in the absence or presence of SWNT. In both cases, we found ayellow material at the top of the flask (Fig. 2). UV-vis absorption spectroscopy and 1H NMR
indicate that the yellow material was dmC12. These results indicate dmC12 has sublimability
and show our concept; sublimation can be a useful way to remove the surfactant from SWNT
surfaces. Calculated saturated vapor pressure of dmC12 is 0.08 Pa at 250°C (Fig. 3) measured
by the vapor pressure evaluation system VPE-9000 (under high vacuum 2.1×10-3 Pa). In thistest, no residue was visually observed (98% weight decrease).
In the presentation, we would like to discuss the further improving the sublimation
property of a flavin compound because thermal reactions compete with sublimation around
250°C under the practical low pressure (0.65-3×103Pa), unfortunately. We observed a red
viscous material at the bottom of the flask. Considering the chemical structure, the long linear
alkyl chain of dmC12 is a steric repulsion site. It is common that saturated vapor pressure ofbranched hydrocarbons is higher than that of straight chained hydrocarbon. It suggests that
there is room to lower the sublimation temperature by changing the chemical structure.
a)b)

C12H25
N
N

N

O
NH

O

Fig.1 a) Chemical structure of dmC12.
b) Photograph of the SWNT
suspensions in toluene in the presence(left) and absence (right) of dmC12(scale bar=1 mm).

Fig.2 Photo of yellow material
at the top of the flask.

[1] Y. Kato et al. Chem. Lett. (2020), accepted.
Corresponding Author: T. Yamada
Tel: +81-29-861-8435, Fax: +81-29-861-4851
E-mail: takeo-yamada@aist.go.jp- 99 -

Fig.3
Saturatedvapor
pressure plot of dmC12.

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2P-26
Study of CVD growth mechanism of graphene on a-plane sapphire○Yuki Ueda1, Jumpei Yamada1, Takahiro Maruyama2, and Shigeya Naritsuka1
1

Department of Materials Science and Engineering, Meijo University, Nagoya 468-8502, Japan2
Department of Applied Chemistry, Meijo University, Nagoya 468-8502, Japan

Direct growth of graphene on an insulating substrate has been studied to avoid thetransfer process, which bring many problems upon industrial applications. Conventionally, cplane sapphire is widely used as a growth substrate. Saito et al. demonstrated that the quality ofgraphene grown on a-plane sapphire was better than that grown on c-plane sapphire [1].
However, graphene growth on a-plane sapphire was rarely reported, and its growth mechanism
has not been clarified yet. In this study, the influence of growth pressure on graphene CVD
growth on a-plane sapphire is investigated for clarifying its growth mechanism.
Graphene was directly grown on a-plane sapphire at 1250 oC by low-pressure CVD
without metal catalyst. Mixture gas of N2, H2, and 3-Hexyne was flown to a reactor for thegrowth of graphene. Growth pressure was chosen 5 and 50 kPa.
Figure 1 shows the growth pressure dependence of Raman spectra. In both cases, thetotal gas flow rate, 3-Hexyne partial pressure, and H2 partial pressure were the same. In the caseof 5 kPa, the obtained D, G, and G' peaks show that graphene was already grown at 1 h. On theother hand, in the case of 50 kPa, graphene was not grown even at a longer growth time of 3 h.
Figure 1 (b) and (c) show the surface AFM images of samples grown at growth pressures of 50
kPa and 5 kPa, respectively. The surface of the sample grown at 50 kPa was flat while that of
the sample grown at 5 kPa was rough. These results indicate that a large amount of atoms of
the sapphire surface were thermally desorbed during CVD when the growth pressure was as
low as 5 kPa. As a result, it is considered that the decomposition efficiency of the carbon source
was possibly improved by the catalytic effects of the thermally desorbed Al atoms, leading to ahigh degree of supersaturation for graphene nucleation and growth. On the other hand, when
the growth pressure was as high as 50 kPa, the thermal desorption of Al atoms was suppressed.
Therefore, the degree of supersaturation was insufficient for graphene nucleation because thecarbon source was difficult to decompose by the weak catalytic effect of the sapphire surface.

Figure 1 Growth pressure dependence of Raman spectra (a). AFM images of samples grown at 50 kPa (b)and 5 kPa (c).
Acknowledgement: This work was supported in part by JSPS KAKENHI Grant Numbers 15H03559, 26105002.
[1] K. Saito et al., J. Phys. Chem. C 118, 5523 (2014).
Corresponding Author: Y. Ueda, Tel: +81-52-838-2387, E-mail: 173441501@ccalumni.meijo-u.ac.jp- 101 -

2P-27Heteroatom-doped Nanocarbons as Active Support for IrO2 as an OER
Electrocatalyst○Prerna Joshi, Rohit Yadav, Masanori Hara, Masamichi Yoshimura
Surface Science Laboratory, Toyota Technological Institute, Nagoya, 468-8511, Japan

Increasing demand for renewable energy systems have guided us to look for environmentfriendly and cheaper energy sources. In this regard, hydrogen comes as a promising candidate
which can be obtained by electrochemical water splitting in water electrolyzers (WEs).
However, oxygen evolution reaction (OER) occurring at anode in WEs is kinetically sluggish
and requires the use of Ir based catalysts. Recent research in the field of OER electrocatalysts
focusses on minimizing the overpotential and reduction in the loading amount of the catalyst.
To overcome these problems, tuning the surface of the catalyst is achieved by the use of
conductive nanocarbon supports doped with heteroatoms [1] such as B and/or N which increase
the electrical conductivity and tolerability of the nanocarbon towards electrolyte medium [2].
Present research focusses on the mono (B or N) and bi-atom doping of graphene (B and N) as
support materials and examines its effect on the OER activity of IrO2 nanoparticles (nps).
The synthesis of nanocarbon supports was done via pyrolysis of graphene oxide (prepared bysynthetic graphite via modified Hummers’ method) and the dopant precursor, urea (N), boron
anhydride, BA (B) and urea+ BA (B/N) at 800, 1000 and 1000 oC respectively to yield N-rGO,
B-rGO and B/N-rGO in N2 atmosphere for 60 min. Further, IrO2 nps were decorated via
hydrothermal method on the doped carbon supports. Prepared catalysts were characterized by
X-ray photoelectron spectroscopy (XPS), transmission electron microscopy (TEM), energy
dispersive X-ray spectroscopy (EDX) and were evaluated for their electrochemical activity
towards OER by linear sweep voltammetry (LSV) with rotating disk electrode (RDE) system).
The presence of the respective elements in the catalysts was confirmed by XPS. Further, EDX
analysis confirmed the homogeneity of the dopants and IrO2 on graphene lattice. The average
particle size estimated from TEM for IrO2 nps on N-rGO, B-rGO and B-N-rGO was 1.6, 1.5
and 1.8 nm respectively. Electrochemical analysis was carried out by LSV in 0.5 M H2SO4
solution (Fig. 1). Catalysts with doped
supports (N-rGO, B-rGO and B/N-rGO)
showed low overpotential and better
durability than undoped catalyst (rGO).
These results demonstrate that the use ofheteroatom doped nanocarbon supports
can enhance the electrochemical activity
towards OER.
[1] M. Alattas et al. Scientific Reports, 8, 17689(2018).
[2] T. Reier et al. ACS Catalysis, 2, 1765 (2012).
Corresponding Author: Dr. Prerna Joshi
Tel: +81-52-809-1852, Fax: +81-52-809-1851
Web: https://www.toyota-ti.ac.jp/surface/index.html
E-mail: joshiprerna2011@toyota-ti.ac.jp

Fig. 1. LSV of IrO2 nps decorated on the B-rGO,
N-rGO and rGO sheets.

- 102 -

2P-28Interactions of Nanodiamonds #1: with Ions in their Solutions	 ○Masaya Nemoto1,2, Shusuke Ando1, Yuho Itabashi1, Toshihiko Tanaka1,2,
Yasuhiro F. Miura3, Tetsuya Aoyama2, Atsuya Muranaka2,
Masanobu Uchiyama2,4, Eiji Osawa5
1

Department of Chemistry and Biochemistry, National Institute of Technology,
Fukushima College, 30 Aza-nagao, Tairakamiarakawa, Iwaki, Fukushima, 970-8034, Japan
2
Elements Chemistry Laboratory, RIKEN Cluster for Pioneering Research,
2-1 Hirosawa, Wako, Saitama, 351-0198, Japan
3
Hamamatsu University School of Medicine, 1-20-1 Handayama,
Higashi-ku, Hamamatsu city, Shizuoka, 431-3192, Japan4
	  Graduate School of Pharmaceutical Sciences, the University of Tokyo,
7-3-1 Hongo, Bunkyo-ku, Tokyo 113-0033, Japan
5
Nano Carbon Research Institute Ltd., Asama Research Extension Center,
Shinshu University, 3-15-1 Tokida, Ueda, Nagano, 386-8567 Japan
Detonation nanodiamonds (DND) often sediment1 with ions from their aqueous colloidal
solutions and the interaction with ions should affect the self-assembly of DND. One aspect of
the interaction is that with the ions in biological organs with respect to their applications for
drug delivery systems2. We consider that elementary diamond nanoparticles (EDIAN) should
aggregate a little with ions in the organs and that the aggregates containing drug molecules
will be delivered there.
We prepared sediments with various salts from 0.25wt.% DND solutions（NanoAmando@, NanoCarbon Research Institute Ltd.）and measured each minimum salt
concentration cm where a phase does not containing any DND particles is shown in a test tube
through sedimentation (Table.1). Such a transparent phase was confirmed by the tyndall effectusing a red laser beam. Their cm values are 0.1~3x10-3(mol/kg) , thus being smaller than thosefor sugars and particularly sulfate or sulfonate anions show significantly small values(<5x10-4). Similar results were already reported forcm values of 0.25wt.% DND
some different sufonates.3 Hence the interaction Table1
solutions for various salt additives.
with anions is more important and should be larger(*'
""$! than that with cations.
 !

We consider that crosslinking of positively !

charged EDIAN (ζ-potential: ~+50 meV) can be !
 !

done with negatively charged ions; the negative'!

charge is well delocalized in the larger oxo acids, 
 !
thereby can play an efficient role of the crosslinker.
 !

Salting out of proteins takes place usually at higher 
salt concentrations exceeding 0.01(mol/kg) and its 
precipitating mechanism should be different from %($!)#')!$#( #%(!#')!$#(
that for DND, although the both are likely to be3!)$'#$((multi-polar charged nanoparticles .
')&$'#$(( 
	
  	
  	
 
[1]N.O. Mchedlov-Petrossyan, N. N. Kamneva, A. I. Marynin, A. P. Kryshtal, E. Osawa, Phys. Chem. Chem.
Phys.,, 17, 16186(2015); [2]E.K.Chow, X.-Q. Zhang, M. Chen, R. Lam, E. Robinson, H. Huang, D. Schaffer, E.
Osawa, A. Goga, D. Ho, Sci. Trans. Med., 3.73(2011); [3]A. S. Barnard, E. Osawa; Nanoscale 6, 1188 (2014).
Corresponding Author:Toshihiko Tanaka / Tel: +81-246-46-0810 / E-mail: ttanaka@fukushima-nct.ac.jp- 103 -

2P-29Interactions of Nanodiamonds #2: with Dye Ions in their Solutions○Yuho Itabashi1, Shusuke Ando1, Masaya Nemoto1,2, Toshihiko Tanaka1,2,
Yasuhiro F. Miura2, Tetsuya Aoyama3, Masanobu Uchiyama3,4, Eiji Osawa5
1

Department of Chemistry and Biochemistry, National Institute of Technology,
Fukushima College, 30 Aza-nagao, Tairakamiarakawa, Iwaki, Fukushima, 970-8034, Japan
2
Elements Chemistry Laboratory, RIKEN Cluster for Pioneering Research,
2-1 Hirosawa, Wako, Saitama, 351-0198, Japan
3
Hamamatsu University School of Medicine, 1-20-1 Handayama,
Higashi-ku, Hamamatsu city, Shizuoka, 431-3192, Japan4
	  Graduate School of Pharmaceutical Sciences, the University of Tokyo,
7-3-1 Hongo, Bunkyo-ku, Tokyo 113-0033, Japan
5
Nano Carbon Research Institute Ltd., Asama Research Extension Center,
Shinshu University, 3-15-1 Tokida, Ueda, Nagano, 386-8567 Japan
Doxorubicin(DX, Fig.1) is usually supplied in its hydrochloride salt and it was applied todrug delivery systems of detonation nanodiamonds (DND) for cancer therapy.1 DND
sediment with salts in their aqueous colloidal solutions2 and DX cations also are likely to
induce DND aggregates. One interesting aspect of DX is whether aggregated elementary
diamond nanoparticles (aggregated EDIAN, ~50nm) play an effective role or not in avoiding
serious side effects to hearts or to bone marrow through EPR effect4 of a large drug spiecies
exceeding 10 nm of its size.
However we cannot prepare DND sediments by adding DX to their solutions whereas we
can do by adding carminic acids (CA, Fig.1). Why does the difference takes place? We
prepared sediments with 3 anionic dyes (Fig1, CA, AQ, and MO) from 0.25wt.% DND
solutions（NanoAmando@, NanoCarbon Research Institute Ltd.）and measured each minimum
salt concentration cm where a phase not containing any DND particles is shown in a test tube.
Such a transparent phase was confirmed by the Tyndall effect using a red laser beam. We willthen discuss the difference in sedimentation between DX and CA together with the other 2dyes. Only DX is not a flocculant for the DND solution. We consider that cations are weakerflocculants than anions as shown in our other poster shown this time.

	
  	
 

	
  	
  	
 

Fig.1 Dye molecules and their cm values for a 0.25 wt.% DND aqueous solution : DX (Doxorubicin) ; CA
(Carminic acid); AQ (Sodium Anthraquinone-1-sulfonate); MO( Methyl orange).
; e) PTFE bar.
[1] E.K.Chow, X.-Q. Zhang, M. Chen, R. Lam, E. Robinson, H. Huang, D. Schaffer, E. Osawa, A. Goga, D. Ho,
Sci. Trans. Med., 3.73(2011; [2] N.O. Mchedlov-Petrossyan, N. N. Kamneva, A. I. Marynin, A. P. Kryshtal, E.
Osawa, Phys. Chem. Chem. Phys., 2015, 16186(2015).
Corresponding Author:Toshihiko Tanaka / Tel: +81-246-46-0810 / E-mail: ttanaka@fukushima-nct.ac.jp- 104 -

2P-30            

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3P-1
Highly Selective and Scalable Fullerene-Cation-Mediated Synthesis
accessing Cyclo[60]fullerenes with 5-Membered-Carbon-Ring and their
Application to Perovskite Solar Cells○Hao-Sheng Lin 1, Il Jeon 1, Shigeo Maruyama 1, Yutaka Matsuo 1
1

Department of Mechanical Engineering,The University of Tokyo, Tokyo 113-8656, Japan

In thin-film photovoltaics, cyclo[60]fullerenes have been widely used as electron
acceptors in organic solar cells and as electron-transporting layers (ETLs) in perovskite solar
cells. In particular, cyclo[60]fullerenes as an over-coating layer of metal oxide ETLs havebeen one of the most exploited applications in perovskite solar cells, demonstrating a dramatic
reduction hysteresis and enhancement of the device charge-dynamics. With respect to suchapplications, heterocyclo[60]fullerene, which is one of the most abundant types ofcyclo[60]fullerene, have shown relatively poor performance compared with full-carbon-ring
cyclo[60]fullerenes because of their electrochemical instability. Accordingly,
cyclo[60]fullerenes with a full-carbon-ring, such as 3-membered-carbon-rings (e.g. PC61BM)
and 6-membered-carbon-rings (e.g. ICBA, MIF), have been the preferred choices for theover-coating layers of metal oxide ETLs. However, cyclo[60]fullerenes with a
5-membered-carbon-ring, namely indano[60]fullerenes, have never been demonstrated to datebecause of inefficient synthetic protocols.
In this work, a fullerene-cation-mediated synthesis,1 accessing a new class of
5-membered-carbon-ring cyclo[60]fullerenes with high yields of up to 93% is showcased.
This method utilizes aryl[60]fullerene cations, ArC60+ as intermediates, which are generated insitu by heating the aryl[60]fullerenyl dimers in the presence of CuBr2. In addition,
5-membered-carbon-ring cyclo[60]fullerenes display excellent device applicability when they
are used in perovskite solar cells as over-coating layers of electron-transporting layers. A
power conversion efficiency of 20.7% is achieved thanks to the favorable energy alignment,
optimized substrate design, and electrochemical stability of the 5-membered-carbon-ringfullerenes.2[1] H.-S. Lin, Y. Matsuo Chem. Comm. 54, 11244 (2018).
[2] H.-S. Lin, I. Jeon, Y. Chen, X.-Y. Yang, T. Nakagawa, S. Maruyama, S. Manzhos, Y. Matsuo, Chem. Mater.
31, 8432 (2019).
Corresponding Author: Y. Matsuo
Tel: +81-3-5841-0978
E-mail: matsuo@photon.t.u-tokyo.ac.jp- 106 -

3P-2
Flattening of 2D materials encapsulated by hBN flakes○Takato Hotta 1, Akihiro Ueda 1, Shohei Higuchi 1, Keiji Ueno 2, Kenji Watanabe 3, Takashi
Taniguchi 3, Ryo Kitaura 1
1
2

Department of Chemistry, Nagoya University, Nagoya 464-8602, Japan
Department of Chemistry, Saitama University, Saitama 338-8570, Japan
3
National Institute of Materials Science, Tsukuba 305-0044, JapanThe hBN encapsulation is one of the most important techniques to address intrinsic
properties of 2D materials, such as graphene and transition metal dichalcogenides (TMDs).
Through the encapsulation by hBN flakes, environmental effects arising from substrates andimpurities can be suppressed. Impurities, which are inevitably encapsulated between hBN
flakes and 2D materials, however, prevent us from investigating fundamental properties of 2D
materials. In this paper, to obtain impurity-free hBN-encapsulated 2D materials, we havedeveloped a fabrication technique based on the Nano-squeeze method 1.
We have fabricated hBN-encapsulated single layer MoSe2 by the dry transfer method witha polymer stamp; an exfoliated MoSe2 flake on SiO2/Si substrate was picked up with a hBN
flake, and then the hBN/MoSe2 was transferred onto another hBN flake. Bubble-like
impurities between the layers were removed by squeezing a surface of the stacking structureswith an AFM probe (Brucker, RESPA-40). As you can see in Figure 1, there are almost no
bubbles after the squeezing process. Although there are no the detectable bubbles in the
hBN/MoSe2/hBN, PL spectra at 10 K show strong signals from trions, whose intensity
depends strongly on the force applied in the squeezing process.
Figure 2 and 3 show the force dependence of PL spectra at 10
K and ratio of the PL intensity from excitons and trions,
respectively. The ratio decreases as the force increases,
meaning that applying force leads to increase of charged
impurities on the surface of top-layer hBN. Based on the
results obtained, we put a few-layer graphene on the top of
hBN/MoSe2/hBN before the squeezing process. We found thatthe top graphene effectively screens the charged impurities
induced by the squeezing process and high-quality MoSe2 can Figure 1 AFM image after removing
be achieved. In this presentation, we will show the details of bubbles.
the sample fabrication andresults of characterization,
including PL, Raman andtransport properties.
[1] M. R. Rosenberger, et. al.,ACS Appl. Mater. Interfaces 10,10379-10387 (2018).
Corresponding Author: R. Kitaura,
Tel:+81-52-789-3660,
Fax:+81-52-747-6442,
E-mail:r.kitaura@nagoya-u.jp

Figure 2 Strength dependence of PL

Figure 3 Force dependence of the ratio

spectra at 10 K.

of exciton/trion.

- 107 -

3P-3




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2&.12:74(-*28:940>4&(/5- 108 -

3P-4
Electrical properties of periodically modified graphene○Yuta Taguchi1, Susumu Saito1
1

Department of Physics, Tokyo Institute of Technology, 2-12-1 Oh-okayama, Meguro-ku,
Tokyo 152-8551, Japan

Ever since the production of graphene by exfoliation, electronic properties of graphene andrelated atomic layer materials have been intensively studied. Its high conductivity is ofscientific importance, while the semiconducting behavior of modified graphene has beenstudied theoretically[1,2] and experimentally[3]. Since there are infinite kinds of periodic
structure modification in principle, various electronic properties are expected to be realized.
In the present work, we study the electronic properties of periodically modified graphene
as shown in Fig.1 and Fig.2 . Figure1 shows a system in which structural defects in the shapeof truncated triangles are arranged in the same direction, and Figure2 shows a system in which
structural defects in the opposite direction are additionally arranged. In Fig.1, there is adifference between the numbers of atoms on two sublattices of the original honeycomb lattice.
While in Fig.2, they are the same. Interestingly, electronic properties are considerably different
from each other near the Fermi energy. We mainly discuss the electronic states near the Fermi
energy in these two types of systems including the magnetic properties in some systems.

Fig.1 Hexagonal arrangements of defects

Fig.2 Super honeycomb lattice arrangement ofon the graphene latticedefects[1] T.Matsumoto and S.Saito, J. Phys. Soc. Jpn. 71, 2765 (2002)[2]M.Sakurai, Y.Sakai, and S.Saito, J. Phys: Conf. Ser. 302, 012018 (2011)[3]B.S.Jessen et al. , Nature Nanotech. 14, 340 (2019)
Corresponding Author: Y. Taguchi
E-mail: taguchi.y.ae@m.titech.ac.jp- 109 -

3P-5
In-plane heterostructure of MoS2 polytypes
Ruben Canton-Vitoria1, Ryo Kitaura1
1

Department of Chemistry, Nagoya University, Nagoya 464-8602, Japan.

During the last 7 years scientific community pay attention to 2D MoS2 due to its highphonon-limited mobility 410 cm2/Vs at room temperature and its high quantum yield.
Recently, the combination of MoS2 with others 2D materials e. j. WS2 forming
heterostructures results attractive for developing more advances devices.1,2 However,heterostructures of different phases of MoS2 (2H, 1T and 1T´) still remained unexplored.
In this poster we present a new CVD methodology which provide in-plane heterostructures
involving different polytypes of MoS2. In order to confirm changes in the phase, several
techniques such as Raman mapping or solid PL mapping images were essential. Concretely,characteristic J1-3 nodes are invisible in the semiconducting MoS2 but were found at basal
plane of monolayers, however, they were negligible at the edges (fig. 1a). Based in the
spectroscopic differences between MoS2 phases, Raman mapping clearly distinguishes 2 welldefined domains (fig. 1b). Such results are in harmony with PL intensity maps, showing
strong intensity emission in the semiconducting phase at the edges, but minor or nothing on
the basal plane (fig. 1c). Additional spectroscopic techniques were carried out in order tosupport the present study. Briefly, Raman Pl not only shows 2 orders of magnitude higher at
the semiconducting phase, but in addition, 15 meV blue shift. Deconvolution of Mo and S
bands through XPS clearly shows the presence of 2 phases and AFM unambiguously shows
homogeneous large areas of MoS2, free of impurities, with lower height than 1 nm, which are
in harmony with single layer. The controlling proportion of reagents, time of reaction andposition play a relevant role in controlling the percentage of phases.

Fig.1. (a) Raman at the basal plane (gray) and at the edges (black), (b) Raman mapping showing thesuperposition of J2 peak (gray) and E12g intensities and (c) PL intensity map of in plane MoS2 heterostructure.

Acknowledgements
This project has received funding Japan Society for the Promotion of Science (JSPS) postdoctoral fellowship grant agreement No P 1 9 3 6 8 .

[1] K, Chen, et al. Adv. Mater. 27, 6431 (2015)[2] M, Okada, et al. ACS Nano 12, 2498 (2018)
Corresponding Author: Ryo Kitaura
E-mail: canton.vitoria.ruben@h.mbox.nagoya-u.ac.jp- 110 -

3P-6
Ultra fast growth of monolayer WS2 measured by in-situ monitoring○Tomoya Kameyama1, Toshiro Kaneko1, Toshiaki Kato1,2
1

Graduate School of Engineering, Tohoku University, Sendai 980-8579, Japan
2
JST-PRESTO[1] T. Kato and T. Kaneko: ACS Nano, 8 (2014) 12777.
[2] T. Kato and T. Kaneko: ACS Nano, 10 (2016) 9687.
[3] T. Akama, W. Okita, R. Nagai, C. Li, T. Kaneko, and T. Kato:
Scientific Reports, 7 (2017) 11967.
[4] C. Li, T. Kameyama, T. Takahashi, T. Kaneko, and T. Kato:
Scientific Reports, 9 (2019) 12958.
Corresponding Author: T. Kameyama
Tel: +81-22-795-7046, Fax: +81-22-263-9225,
http://www.plasma.ecei.tohoku.ac.jp/

Max.
Growth
Velocity[mm/s]
Growthvelocity[mm/s]

Crystal Size [mm]Since the discovery of two dimensional (2D) materials, they have attracted intense
attentions because of their ultrathin thickness, unique optical and electrical features, and highmechanical flexibility [1, 2]. Graphene is the most famous example of 2D materials which has
high electrical conductivity. However, graphene is difficult to be applied for practicalapplications for semiconductor devices due to its zero-bandgap structure. Transition metal
dichalcogenide (TMD) is known as another kind of 2D materials, which possess ultrathinthickness as similar as graphene. TMD is expected to be applied on practical semiconductor
devices because it has tunable bandgap structure. Furthermore, bright photoluminescence of
TMD makes them as a promising candidate for next generation optoelectrical applications [3].
To fabricate the high performance optoelectrical devices, it is greatly important to synthesize
single crystal, monolayer, and large scale TMD. Unfortunately, the uncertain growthmechanism of TMD makes it difficult to realize them.
In this study, to reveal the growth mechanism of monolayer tungsten disulfide (WS2),
in-situ monitoring system has been developed, which can directly observe the time evolutionof monolayer WS2 growth [4]. The result of in-situ(a)monitoring implies that WS2 growth might be300
dominated by the transformation from liquid to solid
Max. Growthphase rather than vapor-solid transformation.
Velocity : ~9 mm/s
Furthermore, WS2 growth velocity is found to be very
200
fast (~9 mm/s) (Fig.1 (a)), which is over 100 times
faster than that of typical graphene. The WS2 growthvelocity decreases with an increase in substratetemperature (Fig.1 (b)). This result suggests that WS2
100
growth follows Wilson-Frenkel model, where
chemical potential difference between growing siteand liquid phase precursors is the dominant element
0
300
350
to decide the growth velocity. These findings about
Growth Time [s]growth mechanism of monolayer WS2 should be
useful to synthesis high quality and single crystal WS2(b)in large scale.
16
14
12
10
8
6
4
2
0

800

805

810

820

Substrate
Temperature
(Tsub
) [℃]
Substrate
Temperature[℃]

Fig.1 (a) Crystal size change as afunction of growth time. (b) Histogramof maximum growth velocity as afunction of substrate temperature.

E-mail: tomoya.kameyama.r1@dc.tohoku.ac.jp- 111 -

3P-7
Isotope Labelling Analysis of Additive Gas Effects on
Single-Walled Carbon Nanotube Growth○Bunsho Koyano1, Shun Yamamoto1, Akari Kobayashi1, Ryoya Ishimaru1, Keigo Otsuka2,
Taiki Inoue1, Rong Xiang1, Shohei Chiashi1, Shigeo Maruyama1, 3
1
2

Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan
Nanoscale Quantum Photonics Laboratory, Riken Cluster for Pioneering Research, Wako,
351-0198, Japan
3
Energy NanoEngineering Lab, National Institute of Advanced Industrial Science andTechnology (AIST), Tsukuba, 305-8564, Japan

Single-walled carbon nanotubes (SWCNTs) are carbon materials whose diameter is about
12 nm and expected to be applied to various devices including electronics. However, themechanism of SWCNT growth remains unclear in many ways, which makes it difficult tosynthesize dense and long SWCNTs applicable to practical electronic devices. To elucidate
the growth mechanism, we proposed a method for tracing the growth profiles of individual
SWCNTs by embedding digitally coded isotope labels [1]. This method unveiled various
features of individual SWCNT growth including the root growth mode, monotonic growth
rates, abrupt growth termination, and so on.
In this work, we investigated the effects of additive gases during a pause of a carbon
precursor [2] and also during a pretreatment process [3] on growth of individual SWCNTs. In
the former case, Ar, Ar/H2 or Ar/H2/H2O was introduced during a pause in the supply of
ethanol at growth temperature of 800 C. In the latter case, we pretreated catalyst at 800 Cwith Ar/H2 for 10 min, Ar/H2 for 60 min, or Ar/H2/H2O for 6 min before growth. We
introduced 13C ethanol pulses with three different ratios while introducing 12C ethanol. Raman
mapping was used to analyze G-band downshifts of individual SWCNTs. Growth curves
constructed from Raman mapping images indicated that SWCNTs interrupted with Ar tended
to show no regrowth while those interrupted with Ar/H2 or Ar/H2/H2O showed regrowth (Fig.
1(ac)). In the case of Ar/H2/H2O, SWCNTs were etched catalytically toward their root partsand regrown with enhanced growth rates. Also, we compared incubation time of SWCNTs
grown from catalyst pretreated under three different conditions (Fig. 1(df)). This resultshows longer time reduction and Ar/H2/H2O pretreatment increased incubation time. We also
applied a tree-based machine learning algorithm to evaluate the additive gas effects on
SWCNT growth.

Fig. 1 Growth curves and Raman mapping images of SWCNTs interrupted with (a) Ar, (b) Ar/H2, and (c)Ar/H2/H2O. Distribution of incubation time of SWCNTs grown after pretreatment with (d) Ar/H2 for 10 min, (e)Ar/H2 for 60 min, and (f) Ar/H2/H2O for 6 min[1] K. Otsuka et al. ACS Nano 12, 3994 (2018). [2] B. Koyano etal., Carbon 155, 635 (2019). [3] B. Koyano et al., in preparation. Corresponding Author: S. Maruyama,
Tel: +81-3-5841-6421, Fax: +81-3-5800-6983, E-mail: maruyama@photon.t.u-tokyo.ac.jp- 112 -

3P-8
Electronic property of CNT thin film under external electric field○Yanlin Gao, Susumu Okada

Department of Physics, Graduate School of Pure and Applied Sciences, University ofTsukuba,
Tsukuba, 305-8571, Japan
Owing to unusual structural and electronic properties, CNTs have been regarded as
emerging materials in wide areas of modern technologies. It has been demonstrated that CNTs
work as conducting channels in field effect transistors (FETs) and thermoelectronic devices.
In usual CNT-based devices, the channels consist of mat films of CNTs, which intrinsicallyintersect or align with other CNTs. At the intersectional and aligned regions, the intertube
interaction plays decisive roles to determine the device performance. In our previous work,
we predicted that field inversion occurs at the intersectional region of two CNTs under a weakelectric field. [1,2] Although the aligned CNTs can work as a conducting channel in real
devices, the carrier distribution is still uncertain in densely aligned CNT thin films in the FET
structure. Thus, in this work, to elucidate the carrier distribution in CNT thin films, we studied
the electronic structures of CNT thin films under an external electric field using density
functional theory combined with effective screening medium method (Fig.1)..
Our calculations show that the distribution of accumulated carriers by the electric fieldslightly depends on the field strength, constituent CNT species, and intertube spacing. For thethin films consisting only of semiconducting CNTs under large gate voltage, the carriers areprimarily distributed on the CNT layer at the electrode side with a small carrier penetration
into the opposite CNT layer. In contrast, thecarrier penetration in the CNT layer at the
opposite side of electrode is enhanced under a low
gate voltage. Unlike the cases of thesemiconducting CNTs, for the thin films
containing metallic CNTs, accumulated carrier
distribution strongly depends on the metallic CNT
arrangement with respect to the electrode. In
addition, a large intertube spacing in the thin films
enhances the carrier concentration on the CNT at Fig.1 Structural model of CNT thin film FET.
the electrode side, except in the thin films
containing metallic CNTs.
Reference[1] Taketo Kochi and Susumu Okada, Appl. Phys. Express 9, 085103 (2016)[2] Taketo Kochi and Susumu Okada, Appl. Phys. Express 10, 075101 (2017)

Corresponding Author: Y. Gao
TEL: +81-29-853-5921, FAX: +81-29-853-5924
E-mail: ylgao@comas.frsc.tsukuba.ac.jp- 113 -

3P-9
Hall Effect and weak-localization conduction
in aligned metallic single-walled carbon nanotube thin films○Kanako Horiuchi1, Ryotaro Okada1, Hideki Kawai1, Yohei Yomogida1, Komatsu Natsumi2,
Weilu Gao2, Junichiro Kono2, Kazuhiro Yanagi1
12Department of Physics, Tokyo Metropolitan University, Tokyo 192-0397, Japan
Department of Electrical and Computer Engineering, Rice University, Texas 77005, USA

Hall effect measurements are important for understanding the charge transport mechanisms
and intrinsic carrier mobility in solid. However, in hopping conduction systems, it is notpossible to correctly evaluate carrier density from the hall effect measurements, because
hopping carriers only respond to the electric force, not to the Lorentz force.[1] Transportmechanisms in most of single-walled carbon nanotube (SWCNT) networks are hopping
conductions, thus usually it is difficult to correctly detect hall effect in SWCNT thin films. In
the case of metallic SWCNTs, we can observe weak localization conduction depending on their
network morphology. Previously, we proposed to use aligned metallic SWCNTs for hallmeasurements because weak localization conduction can be observed in doped aligned metallic
SWCNT films. In this study, we developed an approach to correctly measure hall effect inaligned SWCNTs as follows.
First we need to check conduction mechanism along the “perpendicular” direction to thenanotube axis, and to confirm weak localization conduction along the perpendicular direction.
We usually observe weak-localization conduction along the parallel direction in aligned
metallic SWCNT films, but sometimes not along the perpendicular directions. If the conduction
along perpendicular direction was hopping conduction,
we could not correctly observe hall effect even if we usedaligned metallic SWCNT film.
When the conduction along perpendicular direction is
weak-localization, we can observe hall effect in aligned
metallic SWCNT films as shown in Fig. 1. We injected
electrons or holes by electrolyte gating methods, and we
observed the change of the sign of the hall voltage
according to the types of conduction carriers. Weconcluded that the hall effect was correctly detected inaligned metallic SWCNT films when the conduction Figure 1: Hall voltage as a function ofmagnetic field at Vg of 3.2 V (electron
along the perpendicular direction is weak-localization.
conduction) and -2.7 V (hole conduction).
References: [1] Yi et al., Sci. Rep. 6 23650 (2016)
Corresponding to Kazuhiro Yanagi, yanagi-kazuhiro@tmu.ac.jp- 114 -

3P-10Inﬂuence of interlayer stacking arrangements on carrier
accumulation in bilayer graphene ﬁeld eﬀect transistors
Susumu Okada, Yanlin Gao, and Mina Maruyama
Department of Physics, University of Tsukuba, Tennodai, Tsukuba 305-8571, Japan

Field eﬀects on the electronic properties of graphene thin ﬁlms are an important
subject for practical application of these thin ﬁlms. Experimental and theoretical works
demonstrate that an electric ﬁeld modulate the electronic structure of graphene thinﬁlms. A perpendicular electric ﬁeld induces a ﬁnite band gap in bilayer graphene with
the AB interlayer arrangement, where the width of the band gap depends on the ﬁeld
strength. Bilayer graphene with twisted arrangement in a particular mutual angle(i.e., twisted bilayer graphene) exhibits superconductivity under carrier doping via anelectric ﬁeld. Although these works indicate that the electronic structure and carrier
distribution of graphene thin ﬁlms under an electric ﬁeld depend on the mutual stacking
arrangement, the detailed correlation between the electronic properties and the stacking arrangement in graphene thin ﬁlms under a normal electric ﬁeld remains unclear.
Therefore, in this work, we aim to provide theoretical insight into the inﬂuence of theinterlayer stacking arrangement on the electronic structure of bilayer graphene, using
the density functional theory combined with the eﬀective screening medium method.
Our calculations show that the carriers are extended throughout the layers for graphenewith the AB arrangement. Conversely, the carriers are highly localized on the layer
situated at the electrode side for twisted bilayer graphene. In addition to the electronic
structure, the thermal and thermoelectric properties of bilayer graphene is also foundto depend on the stacking arrangement.
Corresponding Author: Susumu Okada (sokada@comas.frsc.tsukuba.ac.jp)- 115 -

3P-11
Study on effects of twist on phonon transport in graphene nanoribbons○Yukihiko Terada1 and Takuma Shiga1,2
1
Department of Mechanical Engineering, The University of Tokyo, Tokyo 113-8656, Japan
2
PRESTO, Japan Science and Technology Agency, Kawaguchi, Saitama 332-0012, Japan
CNT is a significant candidate for various applications (sensor, field emission devises, andso on) [1] because of its many advantages such as high electron mobility, high thermal
conductivity, and flexibility. So far, thermal conductivity and phonon transport inside CNTs
have been extensively investigated by experiments and simulations, and individual CNTs arefound to have quite high thermal conductivity [2,3]. This high thermal conductivity is of course
due to strong sp2 covalent bond, low-dimensionality, and rotational symmetry of cylindricalstructure [3].
From engineering viewpoint, utilization of the superior thermal conductivity of individual
CNTs is demanded for CNT-based bulk materials like films. In addition to lattice imperfections,an aggregation of CNTs forming a film yields many junctions, which consequently increases
overall thermal resistance. Since CNTs have empty space because of their cylindrical structure,encapsulation of substances into the space is one of effective approaches for modulating thermal
properties. In general, encapsulation negatively influences heat conduction because
encapsulated substances not only are scattering centers of phonons in CNTs but also break therotational symmetry. However, influence of encapsulation on heat conduction has not been fully
clarified, thus, it is still worth to exploring nanomaterials which are beneficial for enhancementof thermal conductivity of CNT-based bulk materials.
We here consider a graphene nanoribbon (GNR) as a candidate for the exploration, andinvestigate phonon transport in coherent ballistic regime by the combination of the atomistic
Green’s function[4] and mode-matching methods[5]. Since GNRs encapsulated in CNTs areexperimentally observed to be twisted[6], we evaluate the effect of partial twist on overall
thermal conductance of GNRs by changing a twist angle per length and a number of units oftwisted GNRs. As results, we find that, while thermal conductance is strongly dependent on
specific twist angle, it is surprisingly insensitive to a number of unit cells of twisted GNRs,
which is intuitively opposite to a usual interpretation in terms of Fabry-Pérot interference.

Figure Thermal boundary conductance as a function of (a) length with 180° twist angle and(b) number of unit cells of 180°-twisted GNRs at room temperature.
[1] R.Baughman, et al., Science, 297, 5582 (2002)., [2] V. Lett, et al., Phys. Rev. Lett. 118, 135901 (2017).
[3] L. Lindsay, et al., Phys. Rev. B 82, 161402(R) (2010). [4] W. Zhang, et al., Num. Heat Trans. B 51, 333 (2007).
[5] Z. Ong and G. Zhang, Phys. Rev. B 91, 17 (2015) [6] A. Talyzin, et al., Nano Lett., 11, 10 (2011)
Corresponding Author: Takuma Shiga, Tel&Fax: +81-3-5841-8091, E-mail: shiga@photon.t.u-tokyo.ac.jp- 116 -

3P-12Iron ion-mediated oxidation of coenzyme NADH by carbon nanotubes○Atsushi Hirano, Momoyo Wada, Takeshi Tanaka, Hiromichi Kataura
Nanomaterials Research Institute, National Institute of Advanced Industrial Science andTechnology (AIST), Ibaraki 305-8565, Japan
As-grown carbon nanotube (CNT) materials have been reported to induce oxidative stresson proteins, which is facilitated by metals originating from the catalyst remains [1]. The
oxidation mechanism should be generally applicable to other biomolecules, including
low-molecular-weight compounds. For understanding biological impact of the CNTs, it isimportant to demonstrate the generality of the mechanism. In this study, we examined a redox
reaction of a coenzyme—nicotinamide adenine dinucleotide (NADH) (Fig.1)—with theCNTs; NADH is a biomolecule used in metabolic systems. It was found that the CNTs withthe remaining metals were reduced by NADH, which means that NADH was oxidized by the
CNTs. The reaction was suppressed by the addition of a chelating agent for the metals,
demonstrating that the metals mediate this reaction. The present results thus suggested that
CNT materials with metals can affect biological reactions involving NADH such as
metabolism.
The CNT used in this study was produced by the HiPco process; therefore, the CNT
materials contain iron species as catalyst remains. NADH used as a reductant for the CNTs isa representative biological reductant andhas a NAD+/NADH redox couple with aredox potential of −0.32 V (vs. NHE)
(Fig.1). Fig.2a shows absorption spectraof the CNTs in the presence and absenceof NADH. NADH induced restoration of
the spectrum, indicating reduction of the
CNTs. The effect of NADH was also
NAD+ + H+ + 2e− ↔ NADH (−0.32 V (vs. NHE))
observed in the time courses profiles ofabsorbance at 1250 nm (Fig.2b). Fig. 1 Chemical structures of NAD+ and NADH. R
Importantly, restoration of the spectrum denotes a moiety composed of ribose–ADP complex.
was kinetically suppressed in thepresence of a chelating agent EDTA,
which indicates that the coexisting iron
ions facilitate the redox reaction
between the CNTs and NADH. Similar
profiles were observed for an NADH
analogue—nicotinamide
adeninedinucleotide phosphate (NADPH). The
Fig. 2 Redox reaction of the CNTs with NADH. (a)iron ion-mediated redox reaction should Absorption spectra of the CNTs in the presence andbe associated with biological impacts of absence of NADH. (b) Time courses of absorbance values
the CNTs in cells and animals.
at 1250 nm.
[1] A. Hirano et al. ACS Nano 13, 1805 (2019).
Corresponding Author: A. Hirano
Tel: +81-29-849-1064, Fax: +81-29-861-2786,
E-mail: hirano-a@aist.go.jp- 117 -

3P-13
Hexagonal boron nitride nanosheets for ultrafast membrane filtration○Rasel Das, Pablo Solís-Fernández, Hiroki Ago

Global Innovation Center (GIC), Kyushu University, Fukuoka 816-8580, Japan
Freshwater facilities are continuously shrinking due to the presence of toxic wastewaterpollutants. It jeopardizes the human health, and diminishes the availability of hygienic foods,
drinks and indirectly causes various diseases. Therefore, developing an efficient wastewater
filtration technology is an urgent need. Very recently, amino functionalized hexagonal boron
nitride (h-BN) membranes have shown good pollutants retention ability combined with fast
permeation [1]. However, preparation of functionalized h-BN nanosheets is very difficult andrequires tedious steps due to its chemical inertness.
In this study, we used N-methyl-2- pyrrolidone (NMP)-assisted simple sonication method
to produce exfoliated h-BN nanosheets [2] without prior functionalization. It allowed us tofabricate a highly ordered lamellar h-BN film, having thickness about 3.0 µm onto
polyvinylidene difluoride (PVDF) support membrane, as shown in Fig. 1. This membrane
showed a very high pure water flux of ̴ 360 L m-2 h-1 bar-1 at neutral pH. We also investigatedto increase the water pollutants selectivity of this h-BN membrane by simply tuning the water
pH. It allowed us to achieve a very good methyl orange (MO) rejection >90% at pH 2.0
combined with a high permeation of 433 L m-2 h-1 bar-1. The
mechanism of water flow through h-BN lamellar structureand MO retention was also investigated in details. This
work paves the way for the development of a novel pHresponsive 2D layered material-based new filtration
technology to separate molecules from many industry
effluents, such as water purification, healthcare,bioprocessing, food, and environmental, because of their
low energy consumption (i.e. high water filtration ability).
References[1] C. Chen et al. Nat. Commun. 9, 1902 (2018).
[2] J. N. Coleman et al. Science 331, 571 (2011).

Fig. 1. Fabrication of a lamellar
membrane using exfoliated h-BN
nanosheets for water purification.

Corresponding Author: R. Das
Tel&Fax: +81-92-583-8975
E-mail: r-das@gic.kyushu-u.ac.jp- 118 -

3P-14
Mechanical and electronic properties of copolymers of centrohexaquinaneand cyclooctatetraene○Yasumaru Fujii, Mina Maruyama, and Susumu Okada
Graduate School of Pure and Applied Sciences, University of Tsukuba, 1-1-1 Tennodai,
Tsukuba, Ibaraki 305-8571, Japan
Polyquinane has been attracting much attention as building block of various real andhypothetical carbon allotropes covering all dimensions. Because of the unsaturated 𝜋𝜋electron states of pentagonal ring, covalent networks ofpolyquinane occasionally possess unusual electronic
structures that are absent in the networks sorely
consisting of hexagonal rings. In addition to theelectronic structure, the polyquinane could form
three-dimensional covalent network that exhibits
unusual mechanical properties: The three-dimensional
network consisting only of fused pentagons(pentadiamond) possesses a moderate bulk modulus
and negative Poisson’s ratio, leading to the remarkablemechanical toughness against the anisotropic structuraldeformation. In addition to the pentadiamond, the large
number of possible combinations and arrangements ofpolyquinane and other hydrocarbons causes the richmorphological variety of polyquinane derivatives.
In this work, using the density functional theory
with generalized gradient approximation, wetheoretically designed three-dimensional covalent
networks consisting of centrohexaquinane [Fig1. (a)]and cyclooctatetraene, and investigated their physicalproperties. In these networks, centrohexaquinane andcyclooctatetraene altenately arrangement at thevertexes and faces of cubic lattice, respectively.
Accordingly, the copolymers are three-dimensional
carbon allotropes consisting of both sp2 and sp3 C
atoms. Furthermore, they possess two strcural isomers
with 𝑃𝑃43𝑚𝑚 [Fig1. (b)] and 𝐹𝐹𝐹𝐹3𝑚𝑚 [Fig1. (c)], owing
to two possible arrangements of centrohexaquinane.
Our calculations demonstrated that these coploymers
are metals with large Fermi level DOS. The
mechanical properties strongly depend on theirmorphologies: The copolymer with 𝐹𝐹𝐹𝐹3𝑚𝑚 symmetry
possesses relatively high bulk modulus with negative Fig.1 (a) Centrohexaquinane. Hydrogen
Poisson ratio, while that with 𝑃𝑃43𝑚𝑚 has low bulk is omitted. Optimized structures of! 3𝑚𝑚 and (c)copolymer with (b) 𝑃𝑃4
modulus with negative Poisson’s ratio.
𝐹𝐹𝐹𝐹3! 𝑚𝑚 symmetry. Light and dark grayspheres denote sp3 and sp2 C atoms,
respectively.

Corresponding Author: Y. Fujii
E-mail: yfujii@comas.frsc.tsukuba.ac.jp- 119 -

3P-15Single molecule magnet properties of Tb-dimetallofullerene anions:[Tb2@C80(Ih)]- and [Tb2@C78(D3h)]○Kazuki Yamagishi , Ryuji Higashinaka2, Yuji Aoki2, Koichi Kikuchi1,
1

Yohji Achiba1, Takeshi Kodama1

1

Department of Chemistry, Tokyo Metropolitan University, Tokyo 192-0397, Japan2
Department of Physics, Tokyo Metropolitan University, Tokyo 192-0397, Japan

8

-3

6

x10 /10 emu
Magnetization

4
2

-3

-3

-3
Magnetization/10
emu
x10

Recently, single molecule magnets (SMMs) containing two lanthanide metals in a fullerene
cage have been studied actively. For example, Tb-dimetallofullerenes, Tb2@C79N [1] andTb2@C80(CH2Ph) [2], exhibited the magnetic hystereses at sweep rate 2.9 mT s-1 up to 27 K
and 28 K, respectively. This rather good SMM property originates from the ferromagneticallycoupled spin system inside the cage, [Tb3+ - e- - Tb3+]. From the theoretical calculation [1], it
was suggested that the symmetry of the electrostatic field in the fullerene cage affect the
SMM properties. Therefore, in this study, we synthesized and isolated [Tb2@C80(Ih)]- and[Tb2@C78(D3h)]-, which have carbon cages with no N-substitution and no additional group,and the magnetic properties were measured to investigate the influence of the cage.
Fig.1 and Fig. 2 show M-H curves for [Tb2@C80(Ih)]- and [Tb2@C78(D3h)]- at sweep rate
4.2 mT s-1, and the hysteresis loops were seen up to 29 K and 15 K, respectively. For[Tb2@C80(Ih)]-, the temperature of hysteresis disappearance is almost identical for Tb2@C79N
and Tb2@C80(CH2Ph) although the symmetry of the electrostatic field in the fullerene cage isdifferent. On the other hand, [Tb2@C80(Ih)]- and [Tb2@C78(D3h)]- have rather different
temperatures of hysteresis disappearance.

0

2K
15 K
24 K
29K

-2
-4
-6
-8
-4

-2

0

4

2

Magneticx10 Field/T

Fig. 1 M-H curve of [Tb2@C80(Ih)]-

4

1.5
1.0
0.5
0.0

2.5 K
10 K
15 K

-0.5
-1.0
-1.5
-2

	
 

[1] G. Velkos et al. Angew. Chem. Int. Ed. 58, 5891 (2019).
[2] F. Liu et al. Nature Communications 10, 571 (2019).
Corresponding Author: Takeshi Kodama
Tel: +81-42-677-2530
Fax: +81-42-677-2525
E-mail: kodama-takeshi@tmu.ac.jp- 120 -

-1

0

4

1

Magneticx10 Field/T

2

Fig. 2 M-H curve of [Tb2@C78(D3h)]-3P-16
Attempt to produce Sm-dimetallofullerenes○Naoya Fujita, Koichi Kikuchi, Yohji Achiba, Takeshi Kodama
Department of Chemistry, Tokyo Metropolitan University, Tokyo 192-0367, JapanThe encapsulated lanthanide metals generally tend to take +3 oxidation state inmonometallofullerenes (mono-EMFs) and dimetallofullerenes (di-EMFs). However, in the
mono-EMFs particular case, those encapsulated metals, Sm, Eu, Tm, and Yb, take +2oxidation state. In the previous work, while Tm-di-EMFs were obtained [1], Yb- andEu-di-EMFs were not obtained [2, 3]. The presence of Tm-di-EMFs was understood by thefollowing: Tm can take +3 oxidation state in di-EMFs, because the 3rd ionization energy (IE3)
of Tm is lower enough forming +3 state. Since the IE3 of Sm is lower than that of Tm, it wasthought that Sm-di-EMFs, which have not been reported, might be obtained. In this work,
using an almost identical method previously reported [4], we tried to produce di-EMFs
containing Sm.
First, we carried out the experiment for the system of only Sm and carbon, but noevidence of the presence of Sm-di-EMFs was obtained. Then, we move to the hetero metal
system. The soot was obtained by direct-current arc discharge of Sm/Y/C (Sm:Y:C=2:1:97)
composite rods under a 500 Torr He atmosphere. The raw soot was extracted for 8 h with amixed solvent of triethylamine and acetone. The extract was separated by HPLC using a
C18-AR-Ⅱ column and a Buckyprep-M column, acetone with an ion-pair reagent,
tetrabutylammonium bromide, as an eluent.
Fig. 1 and 2 show 1st- and 2nd-step HPLC chromatograms and LD-TOF-MS spectra ofeach fraction. In the fraction A-1, the peak of Y2C80 was observed but no peaks of SmMC80
and Sm2C80. Similarly, in the fraction A-2, the peak of Y2C78 was observed but no peaks of
SmYC78, Sm2C78. Therefore, it was suggested that di-EMFs containing Sm, SmYCn andSm2Cn, were not produced or not extracted as an anion form if existed in the raw soot. We
also tried Sm/Tb system and the results will be discussed in the symposium.

Fig.1 1st-step HPLC chromatogram

Fig.2 2nd-step HPLC chromatogram and LD-TOF-MS
spectra of each fraction[1] K. Kobayashi, et al. The 54th Fullerenes-Nanotubes-Graphene General Symposium 48(2018).
[2] K. Kobayashi, et al. The 52nd Fullerenes-Nanotubes-Graphene General Symposium 128(2017).
[3] Y. Furiya, et al. The 56th Fullerenes-Nanotubes-Graphene General Symposium 136(2019).
[4] N. Nakatori, et al. The 49th Fullerenes-Nanotubes-Graphene General Symposium 46(2015).
Corresponding Author: Takeshi Kodama
Tel: +81-42-677-2530, Fax: +81-42-677-2525, E-mail: kodama-takeshi@tmu.ac.jp- 121 -

3P-17In vivo evaluation of biodistribution, toxicity and clearance of single wall
carbon nanotubes depending on the dispersants○Ying Xu1, Minfang Zhang1*, Mei Yang1, Masako Yudasaka 1, 2, Toshiya Okazaki1
1

National Institute of Advanced Science and Technology (AIST)
2
Meijo University

The toxicity and biodistribution of carbon nanotubes are believed to depend on their types,
lengths or functionalization degrees. However, it has not been known that the fate of carbon
nanotubes, having similar lengths and no chemical functionalization are different and dependon the types of dispersants. In this study, we have investigated the effect of two different
dispersants on the biodistribution, toxicity and degradation of single-wall carbon nanotubes(CNTs) after intravenous injection into mice for 3 months.
The CNTs used in this study were produced by the super-growth method (SG-CNTs) [1].
The SG-CNTs were oxidized with H2SO4/HNO3 and then dispersed in bovine serum albumin(BSA) (CNT-BSA) or a phospholipid polyethylene glycol (DSPE-PEG) solution (CNT-PEG)
by sonication. The CNT-BSA or CNT-PEG dispersion solutions were intravenously injected
into mice. At five time points of Day 1, 3, 7, 30, 90, the biodistribution of CNTs in the tissuesof lung, liver, and spleen were estimated by an optical absorption measurement method that wedeveloped recently.
The results showed that the tissues of lung, liver and spleen were pigmented to dark or greyon Day1 due to the accumulation of CNTs in them. For livers and spleens, tissues of CNT-BSA
and CNT-PEG injection groups didn’t show much difference in the color, whereas, slightdifference in the quantities of CNTs. Interestingly, for lungs, the color of CNT-PEG injectedgroup was obviously darker than that of CNT-BSA group. And the quantities of CNT-PEG inlung were much larger than that of CNT-BSA. These results indicated that the biodistributionof SWNTs was related to their dispersants. Moreover, the dark color of lungs faded away andthe quantities of CNT-PEG in lung decreased with the increase of post-injection time, indicating
the clearance of CNTs from lungs. This result confirmed our previous study [2]. In addition, no
obvious signs of toxicity were indicated from our measurements of cytokines in blood plasma
and tissue lysates of liver, lung and spleen. The results suggested that the fate of CNTs in living
body was influenced by the dispersants and the clearance of CNTs from lungs is possible. The
reasons for the dependence of biodistribution on the CNT dispersants are currently under study.
[1] K. Hata, et al. Science, 306, 1362 (2004).
[2] X. Xu et al. 56th Fullerenes-Nanotubes-Graphene General Symposium.
Corresponding Author: M. Zhang
Tel: +81-29-861-6758
E-mail: m-zhang@aist.go.jp- 122 -

3P-18
Importance of structural parameters of CNTs for the Pt electrochemical
durability in CNT based Pt electrocatalysts in PEMFCs○Don Terrence Dhammika Weerathunga1,2, Tsuyohiko Fujigaya*1,2,3
1International Institute for Carbon-Neutral Energy Research (WPI-I2CNER), Kyushu
University, 744 Motooka Nishi-ku, Fukuoka 891-0395, Japan2
Department of Applied Chemistry, Graduate School of Engineering, Kyushu University, 744
Motooka Nishi-ku, Fukuoka 819-0395, Japan
3
Center for Molecular Systems (CMS), Kyushu University, 744 Motooka Nishi-ku, Fukuoka
819-0395, JapanThe durability of polymer
electrolyte fuel cells (PEMFC)
is required to be improved
largely [1]. By using carbon
nanotubes (CNT) as catalyst
Fig. 1 CNT/Pt composites of (a) MW25, (b) MW9.5, (c) SW1.5 andsupport in place of carbon black,(d) SW2.5 [3].
improvement of durability wasreported [2]. To explore the structural dependency on the type of CNT for durability,
accelerated durability tests from 1.0 – 1.5 V vs RHE at 0.5 Vs-1 in 0.1 M HClO4 at 25 oC in
half-cell were performed to CNTs listed in Table 1, after loaded with Pt nanoparticles (Fig. 1).
Table 1. List of CNTs
Label*

MW25

MW9.5

SW1.5

SW2.5

Manufacturer

Nikkiso

NanocylMeijo NC

Nippon Zeon

Diameter / nm

20 – 30

8.5 – 10.5

1.2 – 2.8

2.0 – 3.0

Raman ID/IG

0.22

4.29

0.02

0.16

Pt degradation rate (k)

0.32

6.02

3.36

12.65

*(Labels are as MW for Multi-walled CNTs and SW for Single-walled CNTs with mean diameter as the suffix).

[1] S. Ye et al. ECS Trans 16, 2101 (2008).
[2] Y. Shao et al. J. Electrochem Soc. 153, A1093 (2006).
[3] D. Weerathunga et al. Diam. Relat. Mater. 97, 107459 (2019).
Corresponding Author: T. Fujigaya,
Tel. / Fax: +81-92-802-2840,
E-mail: fujigaya.tsuyohiko.948@m.kyushu-u.ac.jp- 123 -

1.7

MW

0

Pt

)

-1

1.6

Pt

(S /S

Electrochemical stability of CNTs is revealed todominate the stability of Pt. MWs having larger
diameter with lower degree of side-wall defects(witnessed by a low ID/IG in Raman as in Table 1)
offered a lower Pt degradation rate (k) than smaller
MWs and SWs (Fig. 2 and Table 1) [3]. Also the onset
temperature in the thermogravimetric analysis andtheir profiles provide an insight for predicting
durability of their Pt composites (not shown) [3].

MW

1.5

SW

1.4

SW

25
9.5

1.5
2.5

1.3
1.2
1.1
1.0
0.9

0

10
20
30
40
Cycle number (x1,000)

50

Fig. 2 (SPt/S0Pt)-1vs cycle number of Pt
composites, where SPt and S0Pt is the
ECSA at a particular cycle number and at
5,000 cycle number respectively, thegradient of the graphs represent the Pt
degradation rate (k) and the values areshown in Table 1 [3].

3P-19A semitransparent terahertz imager made from chemically doped
semiconducting carbon nanotube thin films○Kanae Oi,1 Kou Li,2 Daichi Suzuki,3 Tsuyoshi Kawai,1 Yukio Kawano,2 Yoshiyuki
Nonoguchi1,41Division of Materials Science, Nara Institute of Science and Technology, NAIST, Takayama,
Ikoma, Nara 8916-5, Japan
2
Laboratory for Future Interdisciplinary Research of Science and Technology,
Tokyo Institute of Technology, 2-12-1 Ookayama, Meguro-ku, Tokyo, 152-8552, Japan
3
Quantum Effect Device Research Team, Center for Emergent Matter Science, RIKEN, 2-1
Hirosawa, Wako, Saitama, 351-0198, Japan
4
JST PRESTO, 4-1-8 Honcho, Kawaguchi, Saitama 332-0012, Japan

Sensing devices with terahertz (THz) wave have a great potential for the use in
nondestructive inspection. Most of them rely on Si and compound semiconductor devices.
Very recently, the photothermoelectric effect of single wall carbon nanotube (SWCNTs) has
been employed to develop flexible THz imagers that can sense real 3D objects [1]. Herein we
utilize semitransparent semiconducting (sc-) SWCNT thin films with excellent thermoelectric
properties for the construction of semitransparent THz detectors.
We dispersed SWCNTs in toluene using poly(9,9-di{2-[2-(2-methoxy-ethoxy)ethoxy]
ethyl}fluorenyl-2,7-diyl) (PFEtO3). This SWCNTs dispersion was then used to form
semitransparent thin films (~300 nm) on PET substrates. The doping level was modulatedwith a p-type dopant (silver bis-(trifluoromethanesulfonyl)imide) and an n-type dopant(KOH/15-crown ether).
The S11 absorption in the near infrared (NIR) gradually bleached and the broad peak (Ip) in
the FIR evolved, depending on the concentration of dopant (Fig.1(a)). Assuming that the
product of THz absorption and power factor is the relative sensitivity of devices, SWCNTs
films has high sensitivity in the wide dopant concentration range (Fig.1(b)). Based on thisresult, we evaluated the noise equivalent power (NEP) of on-tip p–n junction devices
implementing doped SWCNTs films. Along with this, we successfully demonstrated thetwo-dimensional inspection of X-shape metal tapes behind opaque objects (plastic plate andblack tape) by scanning the detector at 29 THz (Fig.1(c)).

Fig.1 (a) NIR-to-FIR spectra of sc-SWCNT films dependent on p-doping concentration. (b) Relationshipbetween sensitivity and p-dopant concentration. (c) An inspection image of a metal tape acquired at 29 THz.
[1] D. Suzuki, S. Oda, and Y.Kawano, Nat. Photonics, 10, 809-813 (2016).
Corresponding Author: Yoshiyuki Nonoguchi
Tel: +81-743-72-6028, Fax: +81-743-72-6179
E-mail: nonoguchi@ms.naist.jp- 124 -

3P-20Compact Wearable Foot Pressure Sensors from MWCNT Coated
Cotton Fibers for Human Activity and Sporting Performance
Monitoring
Md. Abdul Momin1*, Mohammad Jellur Rahman2 and Tetsu Mieno1

12

Graduate School of Science & Technology, Shizuoka University, Shizuoka 422-8529, Japan

Department of Physics, Bangladesh University of Engineering and Technology, Dhaka, BangladeshHigh sensitive compact pressure sensors have been developed using multiwall carbon nanotube(MWCNT) coated cotton fibers. The performance of the sensors is optimized by varying theconcentration of MWCNTs and the thickness of the total fibers. Water-dispersible MWCNT derivatives
is used to coat cotton textiles with high stability [1]. By the citric-acid and oxygen plasma treatments,
MWCNTs are functionalized and they can easily disperse in water. This method is very safe and ecofriendly. These functionalized MWCTNs are coated on cotton fibers and used as filler material of theforce/pressure sensors. These pressure sensors have sensitivities of 1800.20 kPa-1 in the range of forces
F= 1 mN100 N (p= 8.84 Pa884 kPa) [2]. These new pressure sensors have short activation andrelaxation time. The reproducibility of the load cells in pressure measurements is observed, and highreproducibility under different harsh ambient conditions is demonstrated, as well as high durability intests involving more than 11,200 repeated compression/relaxation cycles. The efficiency of the sensors
remains almost the same at low and high temperatures and under low- and high-humidity conditions.
The load cells can measure characteristic signals corresponding to walking, jogging, jumping andstanding conditions and the center of gravity of a human foot during standing, walking and running.
Schematic of sensors and recorded signals during a running are shown in Fig. 1 and Fig. 2. Therefore,
the load cells have, strong potential to be used as wearable force (or pressure)-monitoring devices, forhealthcare tests, rehabilitation, real-time sports activities, and robot technologies.
[1]

Md. J. Rahman, T. Mieno, J. Nanomater., 2014, Article ID 508182 pp. 19 (2014).

[2]

M. A. Momin, Md. J. Rahman, Tetsu Mieno, J. Nanomater, 2019, Article ID 7658437 pp. 1-15 (2019).

Fig.1: The 3 sensors are set in a shoe insole.

Fig. 2: Force signals of the 3 sensors during running.

*Corresponding author: Md. Abdul Momin
E-mail: mamomin89bd@gmail.com, Mobile: +8108041265887- 125 -

3P-21
Activation of Alkane for CVD Growth of Single-Wall
Single-Wall Carbon
CarbonNanotubes○
Pengfei Chen1, Mengju Yang1, Rei Nakagawa1, Hisashi Sugime1, Hitoshi Mazaki22,○Pengfei

Suguru Noda1,3,*

1Department of Applied Chemistry, School of Advanced Science and Engineering,
WasedaTokyo 169-8555,
169-8555, Japan
Japan
Waseda University, 3-4-1 Okubo, Shinjuku-ku, Tokyo
2
Central TechnicalTechnical Research Laboratory, JXTG Nippon Oil & Energy Corporation, 8CentralChidori-cho, Naka-ku, Yokohama, Kanagawa 231-0815, Japan
33
Waseda Research Institute for Science and Engineering, Waseda University,
WasedaUniversity, 3-4-1
3-4-1
Okubo, Shinjuku-ku, Tokyo 169-8555, Japan
Nowadays C2H2 is one of the commonly used carbon sources for the growth of singlewall carbon nanotubes (SWCNTs) due to its high activity [1]. However, the large-area
synthesis of SWCNTs is still a problem because theH22 supply at high concentrations
the C
C22H
easily causes the catalyst deactivation [2]. We proposed the control of gas-phase reactions
by combining two carbon sources of C22H22 and C2H4, which yielded SWCNTs at an
improved areal yield [3]. In this study, instead of using the alkyne or alkene, weinvestigated less reactive alkane as the carbon source. Compared to the C 2H 2, n-hexane(n-C6H14) can be a better candidate because of the lower price and easier storage in liquidstate. We studied the gas-phase reactions by gas chromatography (GC) and gas-phasekinetic simulation (CHEMKIN) to determine the factors that influence the SWCNT
growth. We first checked the CNT synthesis using the combinatorial catalyst (0.2-5 nm
Fe on 15 nm AlOxx) [2] and found that SWCNTs grow from thin Fe layer when n-C6H14
Then we(2 vol%) is fed with H2 at relatively high concentrations (20-40 vol%) (Fig. 1a). Then
examined the large-area synthesis of SWCNTs using the 18 substrates (1×1 cm2 ) with 0.7
nm Fe, and found that SWCNTs was produced at a higher average yield of 1.8 mg cm-2
from n-C6H14 (Fig. 1b) than from C2H2 (1.4
(1.4 mg
mg cm-2-2). The analysis of the gas-phase
species showed that C22H22 forms from n-C6H14 at a concentration similar to the optimum
is anan effective
effective carbon
carbonC2H2 concentration (0.3 vol%) in our previous works [2,3]. n-C66H14
14 issource that yields C2H2 in situ for the large-area synthesis of SWCNTs.
SWCNTs.

forests grown
grown fromfrom 22 vol%vol% n-C
n-C66H
H1414 with different H 2
Fig. 1: (a) Side-view images of the CNT forestsof thethe SWCNTs
SWCNTs grown
grown with
with 2020 vol%vol% H
H22 and 0.7
concentrations on Fe (gradient)/AlOx/Si. (b) Areal mass of
nm Fe. CVD was carried out at 800 °C for 30 min.
K.K.
Hasegawa
andandS. Noda,ACSACS
Nano
5, 975[1] H. Sugime
Sugime andand S.S.Noda,
Noda,Carbon
Carbon50,
50,29532953(2012).
(2012).[2][2]Hasegawa
S. Noda,Nano
5, 975
T. SatoSato etet al.,
al., Carbon
Carbon 136,
136, 143
143 (2018).
(2018).
(2011). [3] T.
Tel: +81-3-5286-2769,+81-3-5286-2769, E-mail:E-mail: noda@waseda.jp
noda@waseda.jp
Corresponding Author: S. Noda, Tel:

- 126 -

3P-22Synthesis of aligned carbon nanotube arrays on quartz wool andits morphological characterization○Nobutomo Yamaguchi, Dai Goudo, Kiyofumi Yamagiwa
Graduate School of Science & Engineering, Teikyo University of Science,
Adachi, Tokyo 120-0045, Japan
Carbon nanotubes (CNTs) are generally synthesized by chemical vapor deposition (CVD)
using hydrocarbons derived from fossil fuels, such as ethylene, benzene, and alcohols, ascarbon sources. Meanwhile, Ando et al. has developed camphor CVD techniques using
camphor (C10H16O), which is a natural tree-derived carbon source [1]. Camphor CVD systems
are promising, given their environmental friendliness and high mass productivity [2]. In thisstudy, CNTs were synthesized on various Silicon-based substrates to examine the effects ofsubstrates on the morphology and yields of CNTs.
CVD was performed using camphor and ferrocene as the carbon source and the catalyst
precursor, respectively. Silicon-based substrates (silicon wafers, quartz wools, and quartz
filter papers) were placed at the center of a ceramic tube in the CVD furnace. The ceramic
tube was heated to 750C (synthetic temperature) for 15 min (synthetic time) under flowing
Ar gas. After the synthesis, the products on the substrate were examined by scanning electron
microscopy (SEM) and transmission electron microscopy (TEM).
Each substrate resulted in a distinctive CNT morphology. Figure 1 shows SEM images ofaligned CNT arrays grown on
the surface of quartz wool fibers
as an example. The arrays were~100 m in length and haverippled plate-shaped structures.
TEM images (not shown here)
5 mindicate that the arrays arecomposed of multi-walled CNTs
with outer diameters of 10-50
nm. In typical applications, thearrays are expected to be
self-supporting thin CNT films,
and this is accomplished byapplying a proper exfoliation
100 mprocess.
The CNT yield and formation
mechanism of the structure will Fig. 1. SEM images of aligned CNT arrays grown on quartz wool.
be discussed in the presentation.
Inset shows high magnification SEM image of the arrays.
[1] M. Kumar and Y. Ando, Chem. Phys. Lett., 374, 521 (2003).
[2] M. Kumar and Y. Ando, J. Nanosci.Nanotechnol., 10, 3739 (2010).
Corresponding Author: K. Yamagiwa
Tel: +81-3-6910-1010
E-mail: yamagiwa@ntu.ac.jp- 127 -

3P-23
Separate control of catalyst and source gases in synthesisof boron nitride nanotubes by chemical vapor deposition○Hiromu takahashi1, Tetsuro Sawada1, Tomohiro Sei1, Mayu Asaka1, Toshio Osawa1,
Hisashi Sugime1, Suguru noda1,2
1

Department of Applied Chemistry, 2Waseda Research Institute for Science and Engineering,
Waseda University, Tokyo 169-8555, Japan.

Boron nitride nanotube (BNNT) has excellent properties such as high mechanical strength,
high thermal stability, high thermal conductivity and so on [1]. Applications for thermalinterface material or wiring system are considered, but the high cost of BNNT is currently
making this difficult [1]. In commercial production, BNNT is synthesized by physical vapor
deposition (PVD) [2] using plasma or laser, therefore the producibility is limited due to thedifficulty of the scaling up of the production. To realize the mass production of BNNT at low
cost, chemical vapor deposition (CVD) has been focused by many researchers [1]. Boron
oxide CVD has been widely researched, however the understanding of the growth mechanismof BNNT is limited. In this research, we studied the growth mechanism of BNNT focusing onunderstanding the effect of B sources, NH3 supplement, and catalyst conditions.
As the B source, the mixture of B and metal oxides (e.g. Fe oxide or Mg oxide) were
widely used in previous reports [1]. However, the independent control of B source andcatalyst was difficult because of the mixed B and catalyst sources. In this research, we used
metal-free B sources and catalysts supported on substrates. Fe catalyst with a thickness
gradient was prepared on AlOx/SiO2/Si or graphite substrates using the combinatorial masked
deposition method to examine catalyst conditions carefully (Fig. 1a). B2O2 vapor as the boron
source was generated by heating the mixed powder of B and B2O3 [3] in the CVD reactor. To
avoid the BN formation on the B source, NH3 was supplied through an inner tube at thedownstream of the B source. The reactor was heated under Ar flow, and after reaching1000 °C, CVD was carried out for 10 min by flowing NH3/Ar. After CVD, the reactor wascooled down to ambient temperature under Ar flow.
Nanotubes were observed well on the graphite substrate but poorly on the AlOx/SiO2/Si
substrate possibly due to the reaction of Fe with the latter at 1000 °C. Scanning electron
microscopy (SEM) (Fig. 1b) showed nanotubes with length, density and diameter changing
with Fe thickness. Individual tubes (a)(c) BF
showed layer structure with aninterlayer distance of 0.34 nm that (b)matches BNNT in transmission
electron microscope (TEM) image(Fig. 1b). Tubes contained N as
N
shown by the scanning electrontransmission microscope-energy
dispersive X-ray spectroscopy(STEM-EDS) (Fig. 1c).
Fig. 1. (a) Catalyst structure. (b) SEM images at different positions.
(c) Blight-field image and elemental map of N by STEM-EDS.
[1] P. Ahmad, et al., RSC Adv. 5, 35116 (2015).
[2] K.S. Kim, et al., Semicond. Sci. Technol. 32, 013003 (2017).
[3] Songfeng E., Chem. Phys. Lett. 687, 307 (2017).
Corresponding Author: S. Noda Tel&Fax: +08-3-5286-2768 E-mail: noda@waseda.jp- 128 -

3P-24
Selective dispersion of semiconducting single-walled carbon nanotubes
by using alkyl cellulose○Tomoko Yagi1, Tsuyoshi Kawai 1, Yoshiyuki Nonoguchi 1, 2
1Division of Materials Science, Nara Institute of Science and Technology, NAIST, Takayama,
Ikoma, Nara 8916-5, Japan
2
JST PRESTO, 4-1-8 Honcho, Kawaguchi, Saitama 332-0012, Japan

Single-walled carbon nanotubes (SWCNTs) are classified into metallic carbon nanotubes(m-SWCNTs) and semiconductor carbon nanotubes (sc-SWCNTs). The selective extraction of
sc-SWCNTs is required for the development of efficient electronic devices. Conjugatedpolymers have been used to selectively disperse sc-SWCNTs [1]; however, these polymers are
not suitable for large scale production due to their high production cost. Here we demonstratethat alkyl cellulose can disperse sc-SWCNTs at high selectivity and yield. Alkyl cellulose is asustainable, and environmentally friendly compound
conformable to large-quantity production. We reveal thatthe selectivity changes depending on the side chain
length of alkyl cellulose.
We dispersed SWCNTs in tetrahydrofuran (THF)
using alkyl cellulose with different alkyl chain lengths(R = C2, C4, C6, C12) (Figure 1). We evaluated the Figure 1. Chemical structure of alkyl
selectivity of sc-SWCNTs extraction using UV-Vis-NIR cellulose (R = C2, C4, C6, C12 )spectroscopy with dispersion.
UV-Vis-NIR spectra indicated that the
selectivity of sc-SWCNTs changes dependingon the side chain length of alkyl cellulose.
Particularly, hexyl cellulose selectively
extracted sc-SWCNTs in THF (Figure 2). This
successful separation expectedly relies on the
difference of the polarizability between sc- andm-SWCNTs polymer complexes which can be
modulated by the side chain length of alkyl
cellulose. Selectivity dependences on solvents,
and polymers’ molecular weight along with
CNT diameters are systematically investigated.
We believe that this result will help elucidate Figure 2. UV-Vis-NIR spectra of dispersions
the mechanism of selective dispersion of normalized by S11 using different alkyl cellulose(R = C2, C4, C6, C12) as a dispersant.
SWCNTs by polymer wrapping.
[1] A. Nish et al. Nat. Nanotech., 2, 640-646 (2007).
Corresponding Author: Yoshiyuki Nonoguchi
Tel: +81-743-72-6028, Fax: +81-743-72-6179
E-mail: nonoguchi@ms.naist.jp- 129 -

3P-25
Scaling laws on enhancement of the electric field inside a hollow cylinder○Yuan Tian, Muhammad Shoufie Ukhtary, Riichiro Saito
Department of Physics, Graduate School of Science, Tohoku University,
Sendai 980-8578, Japan
Nanoscale metallic tube with dielectric core (fig.1) is a good model to represent thecharacter of tips used in tip enhanced Raman spectroscopy (TERS) [1]. Further, multishell nanotubes consisting of of semiconductors is predicted being able to enhance theefficiency of photoelectric devices [2]. For such application, the enhancement of electricfield inside the cylinder should be optimized. E. Devaux et.al. showed that theenhancement occurs by the excitation of surface plasmon (SP) [3].However, eventhough the existence of SP in a hollow core is already studied and well proved,
Designing the cylinder which gives a large enhancement is not easy as a function of
frequency or diameter of the core. It is because that we do not have neither analyticalexpression of the enhancement nor the numerical simulation. If the relationship between
the enhancement of electric field, the geometry and the frequency of the light areavailable, we could synthesize the hollow nano cylinder which gives the bestenhancement for a given frequency of light.
In this work, we calculate the
GLHOHFWULF
enhancement of the electric field inside the[[[[[[[
cylinder with different geometries and𝑎𝑎1  𝑑𝑑frequencies of incident light, in which we
PHWDO
solve the Helmholtz equation with incident
light and boundary conditions.
)LJ7KHOD\RXWRIDKROORZF\OLQGHUZLWK 𝑎𝑎1  DV
We obtain the enhancement of electric
WKHLQQHUERXQGDU\UDGLXVDQGGDVWKHWKLFNQHVV
field inside the cylinder as a function of theincident frequency ω (fig.2). We then foundthat the enhancement can be roughly
fitted as a Lorentzian function of ω. The
parameters of the Lorentzian function,such as the maximum enhancement andwidth can be obtained by scaling theenhancement by the thickness and radius of
the hollow cylinder. Further, the ω ofmaximum enhancement is compared withthe dispersion relation of the SPs. Further
Fig.2 Plot of the electric field enhancement as awhich we obtain resonant condition of SP
function of incident frequency ω for a certain
which is relevant to the enhancement. The
geometry. Dot is the result from numericalcalculation, line is the fitting of the result withfitted scaling function of the enhancement
Lorentzian function.
is useful to find the optimized geometry of
hollow cylinder for a given ω.
㻌

Reference:[1] Alexander S. McLeod et.al., Phys. Rev. B 90, 085136 (2014).
[2] Joseph D. Christesen et.al.,Nano Lett.12, 11, 6024-6029 (2012).
[3] U. Schröter, E. Devaux et.al., Phys. Rev. B 64, 125420 (2001).

- 130 -

3P-26
Photoluminescence of Graphene Oxide Enhanced by UV-radiation in
Dioxane○Katsuki Kanazawa1, Masahito Sano 1
1

Depart. of Organic Materials Science, Yamagata University, Yonezawa 992-0038, Japan

Graphene oxide (GO) contains various oxygen-containing groups, such as epoxide, ether,carbonyl and hydroxyl groups attached to graphene hexagonal structures that have beendamaged to some extents by oxidation. As a result, GO has lost the excellent electronic andmechanical properties of graphene, but, it has gained good dispersibility to many polar
solvents and photoluminescence (PL).
GO dispersed in a solvent exhibits PL under UV radiation. Although the oxygen-containing
groups are shown to be responsible for PL, the detailed mechanisms are not yet understood.
When the size of GO is on the order of a few nanometers (sometimes called graphene
nanodots), it has relatively strong blue emission. For GO of micrometer sizes, it emits aroundyellow-to-red region with much weaker intensities. For practical applications of GO’s PL, it isnecessary to increase the emission intensity.
Recently, we have developed Twilightfluorescence (TwiF) microscopy which iscapable of imaging a single-layer graphene
dispersed in solutions. Presently, it is the
only technique to visualize graphene or GO
floating freely in a liquid. We have also
modified the microscope so that a small
portion of the rays under observation is
directed into a spectrometer, making thesimultaneous measurement of a fluorescence Fig.1 Enhanced photoluminescence of GO single
spectrum possible while imaging the target piece in 1,4-Dioxane (a)0sec (b)900sec (c)1800sec
GO sheet.
When
GO
is
dispersed
inN-methyl-2-pyrrolidone, PL remains stably
constant under UV radiation. Surprisingly,
when GO is dispersed in 1,4-dioxane, PL
increases as UV radiation continues (Fig. 1).
TwiF spectroscopy indicates that the longer
wavelengths are enhanced more than the
shorter wavelengths (Fig. 2). We will discusspossible mechanisms of the enhancement at
the presentation.
Corresponding Author: M. Sano
Tel: +81-238-26-3072,
E-mail: mass@yz.yamagata-u.ac.jp

Fig.2
Fluorescence
spectrumofGO
autofluorescence (Inset shows increase influorescence over time at 565, 615, and 655 nm)- 131 -

3P-27
Effects of interactions at the interface between
graphene and quantum dots on their electronic properties○Zen Inoue1, Yasushi Ishiguro2, Alexader Baranov3 , Igor Nabiev4, Kazuyuki Takai1, 2
12

Graduate school of Science and Engineering, Hosei University, Tokyo 184-8584, Japan
Department of Chemical Science and Technology, Hosei University, Tokyo 184-8584, JapanITMO Univ, 49,Kronverksky, St.Petersburg, Russia MEPhI Univ, 31, Kashirskoe, Moscow, Russia

Graphene as 2-dimensional material has attractive electronic properties, such as broad
spectral bandwidth, high electron mobility. However, graphene has relatively low absorbancein spite of its extremely wide-band nature, which limits its application to photodevices [1].
Semiconductor nano crystals in 0-dimension known as quantum dots (QDs) is promising forphotonics applications due to their size-dependent tunable optical properties [2]. To realize aphotodevices using graphene, a method of constructing hybrid structure combining graphene
and QDs has been proposed. But, the mechanism of charge transfer at the interface between
graphene and QDs is not yet understood [3]. In this study, we clarify the interactions at theinterface between graphene and QDs.
CdSe / PbS-QDs were deposited by spin coating on single-layered (1L) graphene obtainedby the mechanical exfoliation. Photoluminescence (PL) measurements were carried out by anspectrometer (LabRAM HR, Horiba) at excitation wavelength of 532 nm at room temperature.
The electric conductivity was measured for a field effect transistor (FET) using 1L graphene asa channel material after annealing in vacuum chamber (<10-4 Pa) , and after following droppingof CdSe QDs on graphene.
Fig.1 shows a comparison of optical microscope (OM) images of single-layer graphene
before CdS / PbS-QDs deposition and PL intensity mapping after QDs deposition. The PL
intensity was lower in the area graphene laid for both kinds of QDs, attributed to the exciton
quenching caused by charge transfer or near-field interactions between graphene and QDs [4].
Fig.2 shows the transfer characteristics of a FET with CdSe-QDs deposited graphene. The
charge neutral point of the FET shifted to the higher gate voltage (hole) side after deposition of
CdSe QDs on graphene. Hole carrier transfer from QDs to graphene is suggested at the interface.

[1] K. Kim, et al. Nature 457, 706–710 (2009).[2] Y. Sun, et al. Scientific Reports 8, 5107(2018)
[3] R. Li, et al. Scientific Reports 6 ,28224(2016). [4] R. Li, et al. Scientific Reports 6 ,28224(2016).

(a)

(c)

(d)

(b)

Fig.1 OM images of graphene on SiO2 (a), (c), andPL intensity mapping of (a), (c) after coating of
CdSe (b), and PbS (d), respectively

Fig.2 Effects of CdSe QDs on FET- 132 -

3P-28First-principles calculation of exciton of transition metal dichalcogenide○Pang Xiaoqi1, Nguyen T. Hung2, Riichiro Saito1
Department of Physics, Tohoku University, Sendai 980-8578, Japan
Frontier Research Institute for Interdisciplinary Sciences, Tohoku University, Sendai 980-8578,
Japan
1

2

Coulomb interaction between a pair of electron and hole influences the optical properties ofmaterials, which is known as excitonic effect. Usually, by measuring absorption spectroscopy, we
can observe the excitonic effect on many materials, especially for 2D materials. In fact, it reflects
the exciton-photon interaction. Although experimental groups report the excitonic properties, thequantitative analysis by the theoretical calculation is not possible for transition metal
dichalcogenide. Therefore, the theorical analysis based on first-principles calculation which cancalculate the exciton-photon interaction, is necessary to explore how excitons effect the opticalabsorption spectral.
In this work, we use Yambo code [1] to calculate the eigen values and eigen vectors of exciton.
The optical absorption of monolayer and heterostructure transition metal dichalcogenide are
discussed by the calculated results. Future by using eigen vector of exciton, we will discuss how
to develop the program of Raman spectra (Fig.1).

Figure 1: The flow chart to calculate resonant Raman intensity including excitonic effect[1] Andrea Marini et all Comput, Phys. Commun. 180, 1392-1403 (2009)
Corresponding Author: Pang Xiaoqi
Tel: +81-22-795-6442, Fax: +81-22-795-6447,
E-mail: pang@flex.phys.tohoku.ac.jp- 133 -

3P-29Theoretic Study on Raman Active Modes of SnS Thin Films○Itsuki Yonemori1, Sudipta Dutta2, Kosuke Nagashio3, Katsunori Wakabayashi1
School of Science and Technology, Kwansei Gakuin University, Sanda 669-1337, Japan
2
Indian Institute of Science Research and Education (IISER) Tirupati, India
3
Department of Materials Engineering, The University of Tokyo, Tokyo 113-8656, Japan1

Tin sulfide (SnS) is recently attracting much attention as thermoelectric material due to its
low crystal density. For the application to the transparent and flexible devices, the single layer
growth and control of the number of layers are demanded. In addition, it has been reported thatSnS thin film has ferroelectricity depending on the number of layers. [1] In order to identify the
number of layers using Raman spectroscopy, it is necessary to analyze the layer number
dependence of phonon vibration mode. In this study, we investigate the phonon vibration modesof SnS thin films using first-principles calculations.
Figure 1(a) shows the crystal structure of bulk SnS crystal. It has orthorhombic structure anddouble layers in unit cell. The interaction between layers is van der Waals forces. In this study,
we performed structure optimization and calculations of electronic states and phonon modes
under Generalized Gradient Approximation (GGA-PBE)[2] using VASP[3] package. Figure 1(b)is the energy band structure for bulk SnS. Bulk SnS is an indirect transition semiconductor witha band gap about 0.64 eV. The electric states near the top of valence bands (bottom of
conduction bands) are dominated S (Sn) atoms. Figure 1 (c) shows the phonon vibration modesat Γ-point for several different layer numbers. The filled circles indicate Raman active modes,
and empty circles indicate Raman inactive modes. As for the Raman active modes close to 300
cm-1, the frequency mode shifts lower frequency with the increase of the number of layers
owing to the interlayer interaction. On the other hand, the Raman active mode near 100cm-1
shifts toward higher frequency with increase of the number of layers, and the Raman activemode disappears in the bulk structure. Thus, it is found that SnS thin films show the strong
layer number dependence in the Raman active mode in the range 100cm-1 to 300cm-1.

Figure (a) Crystal structure of bulk SnS. (b) Energy band structure for bulk SnS. (c) The phonon vibration modefor bulk, AB stacking bilayer and monolayer. Closed (empty) circles indicate Raman active (inactive) modes.

[1] N. Higashitarumizu et. al. (2019), under review.
[2] J. P. Perdew, K. Burke, M. Ernzerhof, Phys. Rev. Lett. 77, 3865 (1996)[3] G. Kresse and J. Furthmüller, Phys. Rev. B, 54, 11169 (1996)
Corresponding Author:
waka@kwansei.ac.jp

K.

Wakabayashi,

Tel:+81-79-565-9751,- 134 -

Fax:

+81-79-565-9729,

E-mail:3P-30
Molecular adsorption effects on the electrical conduction of
MoS2 on surface-modified substrates⃝Y. Minakawa1, T. Umehara1, K. Takai1,2

12Graduate school of Science and Engineering, Hosei University, Tokyo 184-8584, Japan
Department of Chemical Science and Technology, Hosei University, Tokyo 184-8584, JapanThe EF of 2D-materials such as MoS2 all of which constituent atoms lie on the surface can beeasily tuned by the influence of surrounding substances[1]. Thus the surface chemical structureof the substrates also have a great influence on the electronic properties of supported 2Dmaterials[2]. In this study, we evaluated changes in electrical conduction caused by modifying
the surface of a substrate with polymerized organic molecules such as Parylene for MoS2. In
addition, the effect of water molecules on the electrical conduction of MoS2 was also evaluatedusing Parylene substrates in terms of hole doping by oxygen adsorption.
MoS2-FET was fabricated after mechanical exfoliation on a 285 nm SiO2/Si substrate, and thesubstrate deposited with Parylene. The conductivity was measured under oxygen gas or a mixed
gas of oxygen and water adsorption while varying the oxygen partial pressure and adsorption
time. Oxygen adsorption study was also performed while applying Vgate.
Fig. 1 shows the conductivity of MoS2 under adsorption of oxygen and oxygen-water on MoS2
on Parylene/SiO2/Si substrate while changing the partial pressure of adsorbed oxygen. Underboth conditions of oxygen adsorption and oxygen-water co-adsorption, Vth upshift was observedwith increasing oxygen partial pressure, indicating that hole doping occurred. However, the coadsorption of oxygen and water promotes hole doping into MoS2, and a sharp increase in Vth isobserved even with low-pressure oxygen. Fig. 2 shows the adsorption time dependence of ΔVthdue to oxygen adsorption with the different EF of MoS2 modulated during gas adsorption by
applying Vgate. Vth shifts rapidly when +60 V is applied during oxygen adsorption, and hole
doping is promoted. Conversely, when -60 V was applied, the shift of Vth was small, and thehole doping was inhibited. In other words, at +60 V, the activation energy of the reaction inwhich MoS2 emits electrons decreases, whereas at -60 V, the activation energy of the reactionin which MoS2 receives electrons decreases. These results indicate that the charge transfer rate
can be controlled by applying Vgate in MoS2 as similar to graphene[1] Y. Sato, K. Takai, and T. Enoki, Nano Lett., 11 , 8 (2011),[2] K.Yokota et al., Nano Lett. 11, 3669 (2011),

ISD (μA)-60

O2

O +60 V

VSD = 0.1 V

2ΔVth (V)ISD (μA)

20

O2 + H2O

O 0V

10

2

VSD = 0.1

O -60 V
2

-20
0
20
40
Vgate (V)Fig. 1 Effect of gas adsorption on transfer curve

0-40

Corresponding Author: Kazuyuki Takai
Tel: +81-42-387-6138, Fax: +81-42-387-7002
E-mail: takai@hosei. ac. jp

0

30
60
t (min)90

Fig. 2 Oxygen adsorption effect during Vgate application- 135 -

3P-31
Thermal conductivity of low-cost thermoelectric Mg3Bi2○ Nguyen T. Hung1, Riichiro Saito2
1
Frontier Research Institute for Interdisciplinary Sciences, Tohoku University, Sendai
980-8578, Japan2
Department of Physics, Tohoku University, Sendai 980-8578, Japan
Bi2Te3 is known as a commercial thermoelectric (TE) materials because of their highest TE
performance at room temperature compared with other available TE materials. However, theexpensive Te element limits the wider applications of TE devices based on Bi2Te3. We notethat the cost of the TE materials contributes nearly one third of the total cost for the TE device.
Recently, Mao et al. [1] showed experimentally that by replacing Te with Mg, a new TE
material Mg3Bi2 can performs a figure of merit ZT ~ 0.9 at 350K, which is comparable to
Bi2Te3 but much cheaper. Since the ZT value is inversely proportional to thermal conductivity
κ, a low κ value leads to high ZT value, and then high TE performance. Thus theoreticalanalysis of Bi2Te3 is necessary.
In this work, we calculate theoretical
thermal conductivity of Mg3Bi2 byusing the density functional theory(DFT). First, to analyze the nature ofchemical bonding properties, we
perform COHP (crystal orbital
hamilton population) analyses byusing Quantum Espresso program.
Figure 1: (a) Structure of Mg3Bi2. (b) Mg1 and Mg2 coordinations
The COHP results show that thestructure of Mg3Bi2 can be expressed as Mg2+-[Mg2Bi2]2- as shown in Fig. 1, in which Mg1
atom is relatively more ionic while Mg2 and Bi atoms show the covalent bonds. Therefore,
Mg3Bi2 has a structure as a crystal with glass-like, in which κ = κc + κg, where κc and κg arethermal conductivites by crystal and glass, which is called two-channel model [2]. In present
work, κc is evaluated by the lattice anharmonicity with phonon-phonon interaction from DFT,
while κg is calculated by using the Einstein model for glass systems. The theoretical results iswell consistent with experimental data [1] with κ ~ 2 W/mK at 300K.
[1] J. Mao et al., Science 365, 6452 (2019).
[2] S. Mukhopadhyay et al., Science 360, 1455 (2018).
Corresponding Author: Nguyen Tuan Hung
Tel: +81-22-795-6442, Fax: +81-22-795-6447, E-mail: nguyen@flex.phys.tohoku.ac.jp- 136 -

発表索引
Author Index

Author Index<A>
Abe, Naoya
Abe, Ryo
Achiba, Yohji
Adachi, Kento
Ago, Hiroki
Akai, Nobuyuki
Akasaka, Takeshi
Ando, Shusuke
Anisimov, Anton
Aoki, Nobuyuki
Aoki, Yuji
Aoyagi, Shinobu
Aoyama, Tetsuya
Arai, Hayato
Araki, Tsutomu
Asaka, Koji
Asaka, Mayu

2P-14
1P-14
1-12, 2C-1, 2P-18,
2P-19, 3P-15, 3P-16
2P-11
2P-12, 3P-13
1P-25
1P-18
1P-30, 2P-28, 2P-29
1P-13
1P-1
1-12, 3P-15
1-11
1P-30, 2P-28, 2P-29
1P-9
3-9
1-10
2P-23, 3P-23<B>
Bamba, Masanori
Bando, Yoshio
Baranov, Alexader
Bichara, Christophe
Bode, Jeffery W.

1P-12
1-9
3P-27
3S-2
3P-3

<C>
Cami, J.
Canton, Vitoria Ruben
Chen, Pengfei
Cheng, Guoqing
Chiashi, Shohei<D>Das, Rasel
De Silva K. Kanishka H.
Dutta, Sudipta

2C-5
3P-5
2P-22, 3P-21
2P-3
1P-8, 1P-9, 1P-11,
1P-12, 1P-13, 2-2,
3P-7

3P-13
1P-26
3P-29

<E>
Edo, Michiko
En, Lim HongEndo, Takahiko

1P-4
1P-29
1P-29

<F>
Fajardo, Mario E.
Fang, Nan
Fernandez, Pablo S.
Fortner, Jacob
Fujigaya, Tsuyohiko
Fujii, Yasumaru
Fujimoto, Yoshitaka
Fujisaki, Kotaro
Fujita, Naoya
Fukuhara, Kengo
Fukumori, Kenzo
Fukushima, Tomohiro
Funatsu, Kimito
Furukawa, Ko
Furukawa, Makoto
Futaba, Don N.

2P-16
2P-5
2P-12
3-6
2P-20, 3P-18
3P-14
2-4
2P-7
3P-16
2P-8, 2P-10
1P-3
2-5
3-2
2P-19
1P-18
1-2

<G>
Gao, Weilu
Gao, Yanlin
Golberg, Dmitri
Goto, Chigusa
Goudo, Dai
Grunlan, Jaime C.

2P-10, 3P-9
3P-8, 3P-10
1-9
3-2
1P-21, 3P-22
2S-1

<H>
Haga, Taishi
Hamano, TsuyoshiHara, Masanori
Harano, Koji
Hase, Muneaki
Hasebe, Hidetaka
Hashishin, TakahiroHata, Kenji
Hatanaka, Miho
Hayamizu, Yuhei

2-4
2P-21
1P-5, 2P-27
1-4, 3-7, 3P-3
1P-2
2-5
1P-31
1-2, 2P-24
1P-15
2P-30

- 137 -Higashinaka, Ryuji
Higuchi, Mahoko
Higuchi, Shohei
Hikage, Yurina
Hirai, Tadahiko
Hirano, Atsushi
Hirao, Toshio
Hirata, Eri
Hiratsuka, Atsunori
Hirokawa, Sota
Hisama, Kaoru
Homma, Chishu
Horiuchi, Kanako
Hotta, Takato
Hsia, Fengchun
Hung, Nguyen T.
<I>
Ichinose, Yota
Ideue, Toshiya
Iijima, Sumio
Ikuhara, Yuichi
Inoue, Taiki

Inoue, Zen
Isaka, Takuya
Isayama, Miyako
Ishida, Toshiyuki
Ishiguro, Yasushi
Ishihara, Yoshiaki
Ishii, Akihiro
Ishii, Satoshi
Ishikawa, Takahiro
Ishimaru, Ryoya
Ishitsuka, Asumi
Isobayashi, Atsunobu
Isobe, Hiroyuki
Itabashi, Yuho
Iwasa, Yoshihiro<J>
Jeon, IL

1-12, 3P-15
1-3
3P-2
1P-24
1P-1
1P-2, 3P-12
2P-21
1P-6
1-3
2P-12
1P-8
2P-30
2P-10, 3P-9
3P-2
1-9
3-10, 3P-28, 3P-31

Jeon, Sugyeong
Jiang, Hua
Joshi, Prerna

2-1, 2P-8, 2P-10
3-4
2C-3
1P-11
1P-9, 1P-11, 1P-12,
1P-13, 2-2, 3-6,
3P-7
3P-27
1P-25
2P-4
1-10
1P-27, 3P-27
1-8
3-5, 3-6
2P-21
2P-21
3P-7
1P-16
2P-30
2C-6
1P-30, 2P-28, 2P-29
3-4

Kawachi, Kazuhiko
Kawai, Hideki
Kawai, Tsuyoshi
Kawano, Yukio
Kemper, F.
Khaniya, Sharma Aliza
Kikuchi, Koichi

1-5,
3P-1

2P-2, 2P-17,<K>
Kako, Masahiro
Kameyama, Tomoya
Kanazawa, Katsuki
Kaneko, Toshiro
Kanzawa, Shinji
Kasama, YasuhikoKataura, Hiromichi
Kato, Toshiaki
Kato, Yuichi
Kato, Yuichiro K.
Kauppinen, Esko I.

Kimura, Mutsumi
Kimura, Sadahito
Kitabatake, Daiki
Kitamura, Nozomu
Kitao, Takashi
Kitaura, Ryo
Ko, Jeong Won
Ko, Weon Bae
Kobashi, Kazufumi
Kobayashi, Akari
Kobayashi, Junei
Kodama, Takashi
Kodama, Takeshi
Kojima, Kana
Komai, Takaha
Komatsu, Naoki
Komatsu, Natsumi- 138 -

1P-17
1I-1
1P-5, 2P-27

1P-18
3P-6
3P-26
1-7, 3P-6
1P-18
1-11
1-3, 2P-9, 3-1,
3-3, 3P-12
1-7, 3P-6
2P-24
2P-5, 3-5, 3-6
1I-1, 1P-11, 1P-13,
2-2, 2P-2
1-11
3P-9
3-2, 3P-19, 3P-24
3P-19
2C-5
2P-6, 2P-25
1-12, 2P-18, 2P-19,
3P-15, 3P-16
1P-31
1P-6
1-11
1P-15
1P-22
3P-2, 3P-5
1P-17
1P-17
2P-24
3P-7
2P-7
2P-11
1-12, 2P-18, 2P-19,
3P-15, 3P-16
1P-7, 1P-29
2-5
2P-3
2P-10, 3P-9

Komichi, Yuma
Konishi, Teruaki
Konno, Yui
Kono, Junichiro
Kowashi, Satori
Koyano, Bunsho
Kozawa, Daichi
Kubota, Yoshiyuki
Kumamoto, Akinito
Kwon, Eunsang

3-9
2P-21
2P-1
2P-10, 3P-9
1-4
3P-7
3-6
1S-2
1P-11
1-11

<L>
Li, Kou
Li, Qin-Yi
Li, YanLin, Hao-Sheng
Liu, Dongxin
Liu, Ming
Liu, Zheng
Lungerich, Dominik

3P-19
2P-12
3S-3
1-5, 2P-17, 3P-1
1-4
1P-11, 2-2
1P-7, 2P-15
1-4<M>
Ma, Yue
Machida, Tomoki
Machiya, Hidenori
MacLean, Michael
Maeda, Yuta
Maeda, Yutaka
Maejima, Moeno
Maniwa, Yutaka
Maruyama, Mina
Maruyama, Shigeo

Maruyama, Takahiro
Masubuchi, Satoru
Masumoto, Yui
Matsuda, Hiroyuki
Matsuda, Kazunari

Matsui, Jun
Matsuo, Yoshiaki
Matsuo, Yutaka

Momin, Md. Abdul
Momose, Takamasa
Morisawa, Yusuke
Moriya, Rai
Mouri, Shinichiro
Murakoshi, Kei
Muranaka, Atsuya
Muraoka, Yoshimi
Murayama, Tomoko

2P-1
1P-25
1-5, 2P-2, 2P-17,
3P-1
2P-8
2-4
2P-22, 3P-21
3P-20
3P-30
1-11
2P-1
1P-30, 2P-28, 2P-29
1P-30, 1P-31
1-13
1P-20
3-2
1P-7, 1P-10, 1P-29,
2P-15
1P-7, 2P-1, 2P-9,
2P-15, 3-1
3P-20
2P-16
1P-15
2P-4
3-9
2-5
1P-30, 2P-28, 2P-29
1P-3
3-2

<N>
Nabiev, Igor
Nagashio, Kosuke
Nakagawa, Rei
Nakahara, Kana
Nakamura, Eiichi
Nakamura, Junji
Nakamura, Masakazu
Nakamuro, Takayuki
Nakanishi, Yusuke
Nakano, Masaki
Nakashima, Naotoshi
Nakata, Kazuki
Nakayama, Tomohito

3P-27
2P-5, 3P-29
1P-4, 2P-22, 3P-21
1P-25
1-4, 3-7, 3P-3
2S-2
1P-14
1-4, 3P-3
1P-29, 2P-15
1S-1
1-1
1P-22
1P-2

Matsuoka, Yuya
Matsuura, Yuuto
Mazaki, Hitoshi
Mieno, Tetsu
Minakawa, Yuki
Misaizu, Fuminori
Mitsuishi, Masaya
Miura, Yasuhiro F.
Miyamoto, Kazunori
Miyamoto, Reona
Miyamoto, Yoshiyuki
Miyao, Tomoyuki
Miyata, Yasumitsu
Miyauchi, Yuhei

2P-17
2P-4
3-5
1P-22
1P-18
1P-16, 1P-18, 2P-1
2P-18
1P-29, 2P-15
1P-8, 2-3, 3P-10,
3P-14
1-5, 1P-8, 1P-9,
1P-11, 1P-12, 1P-13,
2-2, 2P-2, 2P-17,
3-6, 3P-1, 3P-7
1P-23, 2P-6, 2P-25,
2P-26
2P-4
1P-31
2P-21
Tutorial, 1P-7, 2P-1,
2P-9, 2P-15, 3-1,
3-9

- 139 -

Nakayasu, Takanori
Narita, Shodai
Naritsuka, Shigeya
Nemoto, Masaya
Niidome, Yoshiaki
Nishihara, Taishi
Nishijima, Satomi
Nishino, Akane
Noda, Suguru
Noguchi, Hironaga
Nonoguchi, Yoshiyuki
Nouchi, Ryo<O>
Obata, Yoshinori
Ochiai, Masahito
Ogawa, Shuhei
Ogura, Noritada
Oguri, Kanata
Ohno, Yutaka
Ohshimo, Keijiro
Oi, Kanae
Okada, Daiki
Okada, Hiroshi
Okada, Ryotaro
Okada, Satoshi
Okada, Susumu
Okamoto, Naofumi
Okawa, Shuhei
Okazaki, Toshiya
Okudaira, Saki
Onga, Masaru
Ono, Tomoya
Onodera, Momoko
Ooishi, Yuya
Osawa, Ayato
Osawa, Eiji
Osawa, Taisei
Osawa, Toshio
Otsuka, Keigo
Otsuka, Masaaki

1-13
1P-31
1P-23, 2P-6, 2P-26
1P-30, 2P-28, 2P-29
2P-20
1P-7, 2P-9, 3-1
1P-24
2P-1
1P-4, 2P-22, 2P-23,
3P-21, 3P-23
2P-30
3-2, 3P-19, 3P-24
1-8

Otsuki, Nao

1P-19

<P>
Pandey, Manish
Peeters, E.
Pichler, Thomas
Pratama, Fenda Rizky
Pu, Jiang

1P-14
2C-5
3S-4
1P-28, 3-8
2P-15

<Q>
Qian, Yang
Qin, Feng

1P-11, 2-2
3-4

<R>

Rahman Mohammad Jellur
1P-27
1P-31
1P-26
1-7
1-13
2P-21
1-11
3P-19
1P-15
1-11
3P-9
3-7
1P-8, 2-3, 3P-8,
3P-10, 3P-14
1P-14
1-5
3P-17
2P-1
3-4
1-13
2P-4
1-13
1P-15
1P-30, 2C-4, 2P-28,
2P-29
1P-31
2P-23, 3P-23
2P-5, 3-6, 3P-7
2C-5

<S>
Saida, Takahiro
Saito, Riichiro
Saito, Susumu
Saito, Yahachi
Sakairi, Masatoshi
Sakurai, Shunsuke
Sano, Masahito
Sasaki, Ryo
Sasaoka, KenjiSato, Akito
Sato, Shu
Sawada, Tetsuro
Schipper, Derek
Schweighauser, Luca
Sei, Tomohiro
Sekido, Masaru
Sekimoto, Yuki
Senga, Ryosuke
Seo, Seungju
Sharma, Kamal Prasad
Shawky, Ahmed
Shiga, Takuma
Shigehisa, Yudai
Shimasaki, Masafumi
Shinokita, Keisuke
Shiraki, Tomohiro- 140 -

3P-20

2P-6
1P-28, 3-8, 3-10,
3P-25, 3P-28, 3P-31
2C-2, 2-4, 3P-4
1-10
1P-6
1-2
3P-26
1-13
2P-13, 2P-14
2P-11
1P-12
2P-23, 3P-23
1-6
3-7
2P-23, 3P-23
1P-19
1P-14
3S-4
2P-2
2P-6, 2P-25
1P-13
3P-11
1P-27
1P-7
1P-7, 3-9
2P-20

Smet, Jurgen
Snowdon, Monika
Solís-Fernández, Pablo
Suenaga, Kazu
Sugai, Toshiki
Sugime, Hisashi
Sugimoto, Wataru
Sugizaki, Yoshiaki
Sukanta, Datta
Sun, Keyi
Suzuki, Daichi
Suzuki, Hal
Suzuki, Kohei
Suzuki, Mitsuaki
Suzuki, Ryuji
Suzuki, Ryutaro
Suzuki, Satoru<T>
Tachibana, Masaru
Taguchi, Yuta
Tajima, Kentaro
Takada, Sari
Takahashi, Hiromu
Takahashi, Koji
Takai, Kazuyuki
Takai, Ryoya
Takakura, Akira
Takenobu, Taishi
Tanaka, Takeshi
Tanaka, ToshihikoTang, Dai-Ming
Taniguchi, Takashi
Tenne, Reshef
Terada, Yukihiko
Teshima, Hideaki
Tian, Yuan
Tomo, Yoko
Tong, Wang
Tsuji, Takashi

3-4
1-6
3P-13
3S-4
1-13
1P-4, 2P-22, 2P-23,
3P-21, 3P-23
1-8
2P-30
1I-1
3P-3
3P-19
1P-15
2P-13
2P-1
3-4
1P-25
2P-21

1P-1
3P-4
1P-25
1P-6
2P-23, 3P-23
2P-12
1P-24, 1P-25, 1P-27,
3P-27, 3P-30
1-12
2P-9, 3-1
2P-15
1-3, 1P-2, 2P-9,
3-1, 3-3, 3P-12
1P-30, 2P-28, 2P-29
1-6, 1-9
2P-4, 2P-5, 3P-2
3-4
3P-11
2P-12
3P-25
2P-12
3-10
1-2

<U>
Uchiyama, Fumiaki
Uchiyama, Masanobu
Ueda, Akihiro
Ueda, Yuki
Ueji, Kan
Uemura, Takashi
Ueno, Hiroshi
Ueno, Keiji
Ukhtary, M. Shoufie
Umehara, Taichi
Utsugi, Koichi

1-13
1P-30, 1P-31, 2P-28,
2P-29
3P-2
1P-23, 2P-26
2-1, 2P-8
1P-22
1-11
3P-2
1P-28, 3-8, 3P-25
3P-30
1P-19

<V>
Vishwanath, Pamarti

1P-26

<W>
Wada, Momoyo
Wada, Naoki
Wakabayashi, Katsunori
Wakabayashi, Tomonari
Wang, Guowei
Wang, Pengyingkai
Wang, Sake
Wang, YuHuang
Watanabe, Kenji
Watanabe, Makoto
Weerathunga Don Terrence Dhammika

Wu, Xiaojian<X>
Xiang, Rong

3P-12
1P-7, 2P-15
3P-29
1P-15, 2P-16
3-3
1P-13
3-8
3S-1, 3-6
2P-4, 2P-5, 3P-2
1P-13
3P-18
3-6

Xiaoqi, Pang
Xing, Junfei
Xu, Ying

1P-9, 1P-11, 1P-13,
2-2, 3-6, 3P-7
3-10, 3P-28
3-7
3P-17

<Y>
Yadav, Rohit
Yagi, Takashi
Yagi, Tomoko
Yamada, Jumpei
Yamada, Maho

1P-5, 2P-27
2P-8
3P-24
1P-23, 2P-26
1-2- 141 -Yamada, Michio
Yamada, Takeo
Yamada, Tomoyuki
Yamagishi, Kazuki
Yamagiwa, Kiyofumi
Yamaguchi, Nobutomo
Yamamoto, Daiki
Yamamoto, Ryohei
Yamamoto, ShunYamamoto, Takahiro
Yamanouchi, Kaoru
Yanagi, Kazuhiro
Yang, FengYang, Mei
Yang, Meng-Ju
Yokoyama, Atsuro
Yomogida, Yohei
Yonemori, Itsuki
Yoshida, Akari
Yoshida, ShunYoshimura, Masamichi
Yotsumoto, Satoshi
Yu, YunYudasaka, Masako<Z>
Zak, Alla
Zhang, Minfang
Zhang, Qiang
Zhang, Wenjin
Zhang, Yijin
Zheng, Yongjia
Zhou, Xin

1P-16, 1P-18, 2P-1
2P-24
2P-15
3P-15
1P-21, 3P-22
1P-21, 3P-22
2P-25
1P-1
3P-7
2P-7, 2P-13, 2P-14
1-4
1P-10, 2-1, 2P-8,
2P-10, 3P-9
3S-3
3P-17
2P-22, 3P-21
1P-6
1P-10, 2-1, 2P-8,
2P-10, 3P-9
3P-29
2P-8, 2P-10
2P-19
1P-5, 1P-26, 2P-27
1P-9, 1P-12
2P-17
1P-6, 3P-17

3-4
3P-17
1I-1
2P-15
3-4
1P-9, 1P-11, 1P-13,
2-2
1-9- 142 -

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2020 年 3 月 15 日発行

第 58 回フラーレン・ナノチューブ・グラフェン総合シンポジウム
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