私たちは、先端材料のためのゼルニケ研究所、フローニンゲン大学の財政支援を認める。

ダブルジャイロイド形態を有する1。PS-B-P4VPの作製とキャラクタリゼーション（PDP）錯体<ol><li>秤量ポリスチレン- ブロック -ポリ（4 -ビニルピリジン）（PS-β-P4VP）及びペンタデシルフェノール（PDP、M rは = 304.51グラム/モル）。ジャイロイド形態を得るためには、慎重であるべきであるPDPの量を選択（PDP（P4VPの重量分率）（）P4VP（PDP）は、fブロックは、約あるべきである。0.6線形ABジブロックコポリマーの相図によれば）。通常、PS-B-P4VPの0.15〜0.2グラムは、PS-B-P4VP（PDP）につながるフィルム（ステップ1.3で使用されたペトリ皿の直径は5〜6センチと仮定）50〜100ミクロンの厚さである。以下の式に従ってPDPの量を計算する。 <img alt="式（1）" src="/files/ftp_upload/50673/50673eq1.jpg" /> <img alt="式2" src="/files/ftp_upload/50673/50673eq2.jpg" /> <img alt="式3" src="/files/ftp_upload/50673/50673eq3.jpg" /><br/&gt; <img alt="式4" src="/files/ftp_upload/50673/50673eq4.jpg" /></li><li>クロロホルムに、PS-B-P4VPとPDPを溶解し、室温で数時間のためにそれをかき混ぜる。均質な複合体形成を確実にするために2重量％未満のポリマーの濃度を維持する。 </li><li>ガラスシャーレに溶液を注ぐ。 </li><li>飽和クロロホルム大気中にお皿を置きます。 </li><li>約1週間後、ペトリ皿を取り出します。超分子複合体の膜を形成する。 </li><li> 30°Cで一晩真空中で膜を乾燥させる。 </li><li>特別に設計された容器にフィルムを置き、コンテナから空気を除去した後、窒素でそれを埋める。 1バールの過圧で、N 2雰囲気下、120℃のオーブン中で4日間、膜をアニール。 </li><li>エポキシに埋め込むフィルムの小片を、カットし、40℃で一晩、それを治す</li><li>室温でダイヤモンドナイフを使用して約80nmの厚さにサンプルをミクロトーム。目Eミクロトームセクションでは、水に浮くでしょう。それらをピックアップし、銅グリッド上に配置します。 </li><li>ヨウ素と瓶にミクロトームセクションを含むグリッドを置く。 45分後に試料を染色し、透過型電子顕微鏡の準備ができている。 </li><li> 120 kVの、画像サンプルの加速電圧で動作する透過型電子顕微鏡での染色切片のCuグリッドを挿入します。 </li><li>小角X線散乱用のサンプルホルダーに（ステップ1.7の後に得られる）フィルム片を挿入し、カプトンテープで固定します。 SAXS用のマシンに調製された試料ホルダーを配置します。 X線シャッターを開いて、2次元散乱パターンを獲得する。取得した2次元パターンを統合し、1次元パターンのピークの位置を分析する。 </li></ol>多孔質構造の2。生成とキャラクタリゼーション<ol><li>エタノール（ステップ1.7の後に得られる）フィルム片を入れて3日間、保管してください。 </li><li>サンプルを乾燥させます。 </li><li>前1 H NMR測定のためのサンプルを削減する。 PDP用粉末、PS-B-P4VP粉末、CDCl 3中（ステップ2.2の後）超分子複合体のPS-B-P4VP（PDP）（ステップ1.7の後）、および多孔質膜を溶解する。室温でレコード1 H NMRスペクトルを示す。 </li><li> PS-B-P4VP粉末を分析し、超分子複合体のPS-B-P4VP（PDP）（ステップ1.7の後）、および示差走査熱量測定による多孔質フィルム（ステップ2.2の後）。 1℃/分の加熱/冷却速度、0.5℃の振動振幅、および60秒の振動周期で変調モードを使用します。 -30℃でサンプルを平衡化、熱180℃、-30℃まで冷却し、その後、180℃に再び加熱しC.分析のための第二の加熱サイクルからのデータを使用しています。 </li><li> 70°Cで、室温で8時間及び18時間（ステップ2.2の後に）多孔質試料をガス放出し、77Kでの窒素吸着測定を実行する</li><li>適切なソフトウェア（例えば、WinADを使用P）および得られた等温線を解析するためのモデル。 </li><li> 8時間50℃で（ステップ2.2の後に）多孔質試料を乾燥し、室温で2時間、0.5 Paの圧力でそれを脱気。 </li><li>水銀圧入を行う。 </li></ol>ポリマーテンプレート中3。挿入ニッケル<ol><li>塩化スズ（のSnCl 2、= 189.60グラム/モルのM r）を秤量し、水溶液を調製する（0.1 MのSnCl 2 / 0.1 M HClを、1.896グラムのSnCl 2、0.8 mlのHClを、100mlのH 2 O）。のSnCl 2の完全な溶解を確実にするためにシェーカーを一晩で解決策を置く。 </li><li>塩化パラジウム（PdCl 2を 、M rは = 177.33グラム/モル）を秤量し、水溶液を調製し（0.0014 MのPdCl 2 / 0.25 MのHCl、0.025グラムのPdCl 2を2mlのHClと100mlのH 2 O）。 </li><li>ニッケルめっき浴の一部1を準備します。6.78グラムを量る硫酸ニッケル六水和物（のNiSO 4•6H 2 O、M、R = 2620.85グラム/モル）及び2gのクエン酸ナトリウムせ（Na 3 C 6 H 5 O 7、M rは = 258.06グラム/モル）と水80mlにそれらを溶解する。 828μlの85％乳酸（C 3 H 6 O 3、M rは = 90.08グラム/モル）を添加する。 </li><li>ニッケルめっき浴の一部2を調製アウト：重量0.2グラムのジメチルアミンボラン錯体（（CH 3）2 NHBH 3、M rは = 58.92グラム/モル）と水20mlに溶かし。ボランジメチルアミン錯体は、換気のよいドラフト内で処理する必要があります。 </li><li> 1時間塩化錫（ステップ3.1）の水溶液中で（ステップ2.2の後）多孔質膜を浸す。 </li><li>脱イオン水で十分にフィルムを洗浄します。 </li><li> 1時間塩化パラジウム（工程3.2）の水溶液にフィルムを浸す。 </li><li>脱イオン水で十分にフィルムを洗浄します。 </li><li>ニッケルめっき浴のパート1（3.3）とパート2（3.4）を混ぜる。水酸化アンモニウムを用いてpHを7.0に調整。 </li><li> 1時間ニッケルめっき浴中に膜を浸す。 </li><li>脱イオン水で十分にフィルムを洗浄します。 </li><li>サンプルを乾燥させます。 </li><li>ステップ1.8から1.9で説明したように、電子顕微鏡のためにプレーティングサンプルを準備します。 </li><li>画像ステップ1.11で説明したように、サンプル。 </li><li>高分解能透過型電子顕微鏡における試料のめっき部分を含むCuグリッドを挿入する。高解像度のTEM顕微鏡写真を取得。顕微鏡下でサンプルを観察し、EDX（X線のエネルギー分散分析）による元素分析のための領域を選択します。選択した領域のEDX分析を行い、得られたパターンを分析します。 </li></ol>逆ジャイロイドニッケル泡の4。露出<ol><li> 350℃のオーブンで（ステップ3.12の後）にニッケルめっき膜を入れて、4日に1時間のアップからそれを維持。 </li><li>銀ペーストを用いてサンプルホルダーにサンプルを添付します。 </li><li>走査電子マイクにサンプルを挿入するroscope。サンプルのいくつかの画像を取得する。 </li><li>走査型電子顕微鏡内に試料を挿入します。顕微鏡下でサンプルを観察し、EDXによる元素分析のための領域を選択します。選択した領域のEDX分析を行い、得られたパターンを分析します。 </li></ol>

<ol>
	<li>Erlebacher, J., Aziz, M. J., Karma, A., Dimitrov, N., Sieradzki, K. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Evolution+of+nanoporosity+in+dealloying.">Evolution of nanoporosity in dealloying.</a> Nature. 410, 450-453 (2001).</li><li>Nyce, G. W., Hayes, J. R., Hamza, A. V., Satcher, J. H. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Synthesis+and+Characterization+of+Hierarchical+Porous+Gold+Materials.">Synthesis and Characterization of Hierarchical Porous Gold Materials.</a> Chem. Mater. 19, 344-346 (2007).</li><li>Detsi, E., van de Schootbrugge, M., Punzhin, S., Onck, P. R., De Hosson, J. T. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=On+tuning+the+morphology+of+nanoporous+gold.">On tuning the morphology of nanoporous gold.</a> Scripta Mater. 64, 319-322 (2011).</li><li>Gacoin, T., Lahlil, K., Larregaray, P., Boilot, J. P. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Transformation+of+CdS+Colloids:+Sols,+Gels,+and+Precipitates.">Transformation of CdS Colloids: Sols, Gels, and Precipitates.</a> J. Phys. Chem. B. 105, 10228-10235 (2001).</li><li>Tappan, B. C., Steiner, S. A., Luther, E. P. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanoporous+Metal+Foams.">Nanoporous Metal Foams.</a> Angew. Chem. Int. Ed. 49, 4544-4565 (2010).</li><li>Leventis, N., Chandrasekaran, N., Sadekar, A. G., Sotiriou-Leventis, C., Lu, H. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=One-Pot+Synthesis+of+Interpenetrating+Inorganic/Organic.">One-Pot Synthesis of Interpenetrating Inorganic/Organic.</a> Networks of CuO/Resorcinol-Formaldehyde Aerogels: Nanostructured Energetic Materials. J. Am. Chem. Soc. 131, 4576-4577 (2009).</li><li>Leventis, N., Chandrasekaran, N., Sotiriou-Leventis, C., Mumtaz, A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Smelting+in+the+age+of+nano:+iron+aerogels.">Smelting in the age of nano: iron aerogels.</a> J. Mater. Chem. 19, 63-65 (2009).</li><li>Tappan, B. C., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Ultralow-Density+Nanostructured+Metal+Foams:+Combustion+Synthesis,+Morphology,+and+Composition.">Ultralow-Density Nanostructured Metal Foams: Combustion Synthesis, Morphology, and Composition.</a> J. Am. Chem. Soc. 128, 6589-6594 (2006).</li><li>Ashby, M. F., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Metal+Foams:+a+Design+Guide.">Metal Foams: a Design Guide.</a> Butterworth-Heinemann. , (2000).</li><li>Tekoglu, C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Size+Effects+in+Cellular+Solids.">Size Effects in Cellular Solids.</a> , (2007).</li><li>Amsterdam, E. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Structural+Performance+and+Failure+Analysis+of+Aluminium+Foams.">Structural Performance and Failure Analysis of Aluminium Foams.</a> , (2008).</li><li>Bates, F. S., Fredrickson, G. H. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Block+Copolymer+Thermodynamics:+Theory+and+Experiment.">Block Copolymer Thermodynamics: Theory and Experiment.</a> Annu. Rev. Phys. Chem. 41, 525-527 (1990).</li><li>Hamley, I. W. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> The Physics of Block Copolymers. , (1998).</li><li>Abetz, V., Simon, P. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Advances in Polymer Science. , (2005).</li><li>Hillmyer, M. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanoporous+Materials+from+Block+Copolymer+Precursors.">Nanoporous Materials from Block Copolymer Precursors.</a> Adv. Polym. Sci. 190, 137-181 (2005).</li><li>Mansky, P., Harrison, C. K., Chaikin, P. M., Register, R. A., Yao, N. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanolithographic+templates+from+diblock+copolymer+thin+films.">Nanolithographic templates from diblock copolymer thin films.</a> Appl. Phys. Lett. 68, 2586-2588 (1996).</li><li>Hashimoto, T., Tsutsumi, K., Funaki, Y. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanoprocessing+Based+on+Bicontinuous+Microdomains+of+Block+Copolymers:+Nanochannels+Coated+with+Metals.">Nanoprocessing Based on Bicontinuous Microdomains of Block Copolymers: Nanochannels Coated with Metals.</a> Langmuir. 13, 6869-6872 (1997).</li><li>Chen, S. -. Y., Huang, Y., Tsiang, R. C. -. C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Ozonolysis+efficiency+of+PS-b-PI+block+copolymers+for+forming+nanoporous+polystyrene.">Ozonolysis efficiency of PS-b-PI block copolymers for forming nanoporous polystyrene.</a> J. Polym. Sci. A Polym. Chem. 46, 1964-1973 (2008).</li><li>Thurn-Albrecht, T., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanoscopic+Templates+from+Oriented+Block+Copolymer+Films.">Nanoscopic Templates from Oriented Block Copolymer Films.</a> Adv. Mater. 12, 787-791 (2000).</li><li>Park, M., Harrison, C., Chaikin, P. M., Register, R. A., Adamson, D. H. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Block+Copolymer+Lithography:+Periodic+Arrays+of+~1011+Holes+in+1+Square+Centimeter.">Block Copolymer Lithography: Periodic Arrays of ~1011 Holes in 1 Square Centimeter.</a> Science. 276, 1401-1404 (1997).</li><li>Cheng, J. Y., Ross, C. A., Thomas, E. L., Smith, H. I., Vancso, G. J. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Fabrication+of+nanostructures+with+long-range+order+using+block+copolymer+lithography.">Fabrication of nanostructures with long-range order using block copolymer lithography.</a> Appl. Phys. Lett. 81, 3657-3659 (2002).</li><li>Voet, V. S. D., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Interface+Segregating+Fluoralkyl-Modified+Polymers+for+High-Fidelity+Block+Copolymer+Nanoimprint+Lithography.">Interface Segregating Fluoralkyl-Modified Polymers for High-Fidelity Block Copolymer Nanoimprint Lithography.</a> J. Am. Chem. Soc. 133, 2812-2815 (2011).</li><li>Zalusky, A. S., Olayo-Valles, R., Wolf, J. H., Hillmyer, M. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Ordered+Nanoporous+Polymers+from+Polystyrene-Polylactide+Block+Copolymers.">Ordered Nanoporous Polymers from Polystyrene-Polylactide Block Copolymers.</a> J. Am. Chem. Soc. 124, 12761-12773 (2002).</li><li>Crossland, E. J. W., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=A+Bicontinuous+Double+Gyroid+Hybrid+Solar+Cell.">A Bicontinuous Double Gyroid Hybrid Solar Cell.</a> Nano Lett. 9, 2807-2812 (2008).</li><li>Uehara, H., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Size-Selective+Diffusion+in+Nanoporous+but+Flexible+Membranes+for+Glucose+Sensors.">Size-Selective Diffusion in Nanoporous but Flexible Membranes for Glucose Sensors.</a> ACS Nano. 3, 924-932 (2009).</li><li>Voet, V. S. D., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Poly(vinylidene+fluoride)/nickel+nanocomposites+from+semicrystalline+block+copolymer+precursors.">Poly(vinylidene fluoride)/nickel nanocomposites from semicrystalline block copolymer precursors.</a> Nanoscale. 5, 184-192 (2013).</li><li>Brinker, C. J., Scherer, J. W. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Sol-Gel Science: The Physics and Chemistry of Sol-Gel Processing. , (1990).</li><li>Hsueh, H. -. Y., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Inorganic+Gyroid+with+Exceptionally+Low+Refractive+Index+from+Block+Copolymer+Templating.">Inorganic Gyroid with Exceptionally Low Refractive Index from Block Copolymer Templating.</a> Nano Lett. 10, 4994-5000 (2010).</li><li>Hsueh, H. -. Y., Ho, R. -. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Bicontinuous+Ceramics+with+High+Surface+Area+from+Block+Copolymer+Templates.">Bicontinuous Ceramics with High Surface Area from Block Copolymer Templates.</a> Langmuir. 28, 8518-8529 (2012).</li><li>Riedel, W. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Electroless Nickel Plating. , (1991).</li><li>Mallory, G. O., Hajdu, J. B. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Electroless+Plating:+Fundamentals+and+Applications.">Electroless Plating: Fundamentals and Applications.</a> American Electroplaters and Surface Finishers Society. , (1992).</li><li>Djoki&#263;, S. S. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Modern Aspects of Electrochemistry. , (2002).</li><li>Djoki&#263;, S. S., Cavallotti, P. L. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=.">.</a> Modern Aspects of Electrochemistry. , (2010).</li><li>Crossland, E. J. W., Ludwigs, S., Hillmyer, M. A., Steiner, U. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Control+of+gyroid+forming+block+copolymer+templates:+effects+of+an+electric+field+and+surface+topography.">Control of gyroid forming block copolymer templates: effects of an electric field and surface topography.</a> Soft Matter. 6, 670-676 (2010).</li><li>Hsueh, H. Y., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Nanoporous+Gyroid+Nickel+from+Block+Copolymer+Templates+via+Electroless+Plating.">Nanoporous Gyroid Nickel from Block Copolymer Templates via Electroless Plating.</a> Adv. Mater. 23, 3041-3046 (2011).</li><li>Vukovic, I., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Supramolecular+Route+to+Well-Ordered+Metal+Nanofoams.">Supramolecular Route to Well-Ordered Metal Nanofoams.</a> ACS Nano. 5, 6339-6348 (2011).</li><li>Mao, H., Hillmyer, M. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Macroscopic+samples+of+polystyrene+with+ordered+three-dimensional+nanochannels.">Macroscopic samples of polystyrene with ordered three-dimensional nanochannels.</a> Soft Matter. 2, 57-59 (2006).</li><li>Kobayashi, Y., Tadaki, Y., Nagao, D., Konno, M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Deposition+of+Gold+Nanoparticles+on+Polystyrene+Spheres+by+Electroless+Metal+Plating+Technique.">Deposition of Gold Nanoparticles on Polystyrene Spheres by Electroless Metal Plating Technique.</a> J. Phys. Conf. Ser. 61, 582-586 (2007).</li><li>Finnefrock, A. C., Ulrich, R., Toombes, G. E., Gruner, S. M., Wiesner, U. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=The+plumber's+nightmare:+a+new+morphology+in+block+copolymer-ceramic+nanocomposites+and+mesoporous+aluminosilicates.">The plumber's nightmare: a new morphology in block copolymer-ceramic nanocomposites and mesoporous aluminosilicates.</a> J. Am. Chem. Soc. 125, 13084-13093 (2003).</li><li>Tyler, C. A., Morse, D. C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Orthorhombic+Fddd+network+in+triblock+and+diblock+copolymer+melts.">Orthorhombic Fddd network in triblock and diblock copolymer melts.</a> Phys. Rev. Lett. 94, 208-302 (2005).</li><li>Ranjan, A., Morse, D. C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Landau+theory+of+the+orthorhombic+Fddd+phase.">Landau theory of the orthorhombic Fddd phase.</a> Phys. Rev. E. 74, 011803 (2006).</li><li>Kim, M. I., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Stability+of+the+Fddd+Phase+in+Diblock+Copolymer+Melts.">Stability of the Fddd Phase in Diblock Copolymer Melts.</a> Macromolecules. 41, 7667-7670 (2008).</li></ol>

著者らは、競合する経済的利益を宣言していません。

超分子複合体が正常に秩序金属ナノフォームのための前駆体として適用される。この方法では、重要なステップは、ジャイロイド形態を持つテンプレートすなわち 、適切なテンプレートを取得することである。ブロックコポリマーの相図において、ジャイロイド領域は非常に小さく、それが標的とするのがかなり困難である。これは、従来のブロックコポリマーを出発材料として使用...

6,7 nanosmelting、1-3脱合金、ゾル-ゲルは、4,5近づき 、燃焼合成8：そこ金属ナノフォームの製造のための利用可能ないくつかの技術がある。脱合金プロセスにおいて、出発材料は、通常、例えば、二元合金、銀と金の合金である。少ない貴金属、この場合、銀は、ナノサイズを有する不規則靭帯金多孔質発泡体をもたらす化学的または電気化学的に除去することができる。燃焼合成法では、金属は、その分解中にエネルギーを放出し、金属ナノ発泡体8の形成を駆動するエネルギーの前駆体と混合される。金属発泡体の機械的挙動に関する研究が無秩序のアーキテクチャで応力が全体的なマクロスケール9-11に靱帯ナノスケールから効果的に伝達することができないことを示す。したがって秩序金属ナノフォームのと比較して、優れた機械的特性を有することが期待される無秩序なもの。 ここに示される考え方は、金属ナノフォーム前駆体として順序付けられたナノ構造体に自己組織化ブロックコポリマーを使用することである。球状、円筒状、層状、ダブルジャイロイド、六角形穿孔ラメラなど12-14：ブロック共重合体の組成は、モノマー単位の総数および化学的に接続されたブロック間の反発の程度に応じて、様々な形態は以下のような表示され。また、重合体ブロックは、ナノ多孔質材料15につながる選択的に分解することができる。最も一般的な方法としては、オゾン分解16-18、UV照射19、反応性イオンエッチング20-22、および23-26を溶解。生成された多孔質構造は、様々な無機材料で埋め戻すことができる。金属酸化物（ 例えば SiO 2やTiO 2の ） は 、通常、テンプレートのチャンネル27-29にゾル-ゲル法を介して導入される。エルectrochemical及び無電解めっきは、一般に30-33またはテンプレート上に金属を堆積するために使用される。最後に、残りの重合体等の熱分解2、溶解34,35、UV劣化28,29 を介して 、ポリマー/無機ナノハイブリッドから除去することができる我々のアプローチでは、ポリスチレン- ブロック -ポリ（4 -ビニルピリジン）（PS-β-P4VP）ジブロックコポリマーおよび両親媒性ペンタデシルフェノール（PDP）分子の超分子複合体から開始する。この複合体は、PDP及びピリジン環（図1a）との間の水素結合の結果である。開始ブロック共重合体の組成と添加量は、PDPのように選択されるPSネットワークとP4VP（PDP）マトリックスとの両連続二重ジャイロイド形態で得られた系自己集合（ 図1b）。 PDPの分子は、（選択的にPSネットワーク上にエタノールとP4VPチェーンの崩壊に溶解なる図1c）。続いて、無電解メッキ法を用いて、ニッケルのテンプレート（ 図1d）の細孔内に堆積される。熱分解を介して、残りのポリマーを除去した後、秩序ジャイロイドニッケルナノ発泡体（ 図1eに ）が得られる。

<table border="1">
 <tbody>
 <tr>
 <td>REAGENTS:</td>
 <td></td>
 <td></td>
 <td></td>
 </tr>
 <tr>
 <td>PS-b-P4VP, CAS: 26222-40-2</td>
 <td>Polymer Source Inc.</td>
 <td>P9009-S4VP 
 P136-S4VP 
 P5462-S4VP 
 P3912-S4VP</td>
 <td>additional information are provided in a separate table</td>
 </tr>
 <tr>
 <td>PDP</td>
 <td>Aldrich</td>
 <td>P4402-100G-A</td>
 <td>recrystallized twice from petroleum ether</td>
 </tr>
 <tr>
 <td>SnCl2</td>
 <td>Acros Organics</td>
 <td>196981000</td>
 <td></td>
 </tr>
 <tr>
 <td>PdCl2</td>
 <td>Aldrich</td>
 <td>76050</td>
 <td></td>
 </tr>
 <tr>
 <td>NiSO4 x H2O</td>
 <td>Sigma-Aldrich</td>
 <td>227676</td>
 <td></td>
 </tr>
 <tr>
 <td>lactic acid</td>
 <td>Aldrich</td>
 <td>W261106</td>
 <td></td>
 </tr>
 <tr>
 <td>citric acid trisodium salt</td>
 <td>Sigma-Aldrich</td>
 <td>C3674</td>
 <td></td>
 </tr>
 <tr>
 <td>borane dimethyl amine complex</td>
 <td>Aldrich</td>
 <td>180238</td>
 <td></td>
 </tr>
 <tr>
 <td>PS-b-P4VP catalogue number</td>
 <td>Mn (PS), g/mol</td>
 <td>Mn(P4VP), g/mol</td>
 <td>PDI</td>
 </tr>
 <tr>
 <td>P9009-S4VP</td>
 <td>24000</td>
 <td>9500</td>
 <td>1.1</td>
 </tr>
 <tr>
 <td>P136-S4VP</td>
 <td>31900</td>
 <td>13200</td>
 <td>1.08</td>
 </tr>
 <tr>
 <td>P5462-S4VP</td>
 <td>37500</td>
 <td>16000</td>
 <td>1.3</td>
 </tr>
 <tr>
 <td>P3912-S4VP</td>
 <td>41500</td>
 <td>17500</td>
 <td>1.07</td>
 </tr>
 </tbody>
</table>

gyroid nickel nanostructures from diblock copolymer supramolecules

熱伝導性および導電性を、それらが触媒的に活性であり、しかも、高い気孔率、高い表面対体積及び強度対重量比を有する - ナノ多孔質金属発泡体は、特性の独特の組み合わせを有する。残念ながら、金属ナノ構造体の調製のための一般的なアプローチは、それらの機械的特性に悪影響を与える可能性のある、非常に不規則なアーキテクチャを有する材料をレンダリングする。ブロックコポリマーは、順序付けられたナノ構造体に自己組織化する能力を有し、秩序金属ナノフォームの製造のためのテンプレートとして適用することができる。ここでは、ブロックコポリマーベースの超分子複合体の応用を説明-ポリスチレン- ブロック -ポリ（4 -ビニルピリジン）（ペンタデシルフェノール）PS-β-P4VP（PDP） -秩序ニッケルナノ発泡体のための前駆体として。超分子複合体は、従来のブロック共重合体と同様相挙動を示し、二連続ジャイロイド形態学のウィットに自己組織化することができますP4VP（PDP）がマトリクス状に配置されたH 2のPSネットワーク。 PDPは、金属で埋め戻しすることができる多孔質構造の形成をもたらすエタノールに溶解することができる。無電解めっき技術を用いて、ニッケル、テンプレートのチャンネルに挿入することができる。最後に、残りのポリマーは、逆ジャイロイド形態を有するナノ多孔性ニッケル発泡体で得られたポリマー/無機ナノハイブリッドの熱分解を介して除去することができる。

代表超分子複合体の超分子複合体のPS-B-P4VP（PDP）は、xをTEMおよびSAXSによって検査されるの形態図2Aおよび図2Bディスプレイの典型的なジャイロイドパターン：ダブル波と表現することが知られているワゴンホイールパターンそれぞれ（211）を介して凸とジャイロイド単位セルの（111）面、。 P4VP（PDP）xブロックドメインによるヨウ素染色に暗く見えるながらPS?...

Watch this Scientific Journal Video about Gyroid Nickel Nanostructures from Diblock Copolymer Supramolecules at JoVE.com

Gyroid Nickel Nanostructures from Diblock Copolymer Supramolecules

この記事では、自己組織化ジブロック共重合体ベースの超分子から得たナノポーラステンプレート上に無電解金属堆積経由秩序ニッケルナノフォームの製造が記載されている。

ジブロック共重合体超分子からジャイロイドニッケルナノ構造

Nanoporous metal foams possess a unique combination of properties - they are catalytically active, thermally and electrically conductive, and furthermore, ...

gyroid-nickel-nanostructures-from-diblock-copolymer-supramolecules

Research

JoVE Journal

Chemistry

12.3K ビュー.  University of Groningen. この記事では、自己組織化ジブロック共重合体ベースの超分子から得たナノポーラステンプレート上に無電解金属堆積経由秩序ニッケルナノフォームの製造が記載されている。 

ビデオ: Gyroid Nickel Nanostructures from Diblock Copolymer Supramolecules

Nucleoside Triphosphates - From Synthesis to Biochemical Characterization

The traditional strategy for the introduction of chemical functionalities is the use of solid-phase synthesis by appending suitably modified phosphoramidite precursors to the nascent chain. However, the conditions used during the synthesis and the restriction to rather short sequences hamper the applicability of this methodology. On the other hand, modified nucleoside triphosphates are activated building blocks that have been employed for the mild introduction of numerous functional groups into nucleic acids, a strategy that paves the way for the use of modified nucleic acids in a wide-ranging palette of practical applications such as functional tagging and generation of ribozymes and DNAzymes. One of the major challenges resides in the intricacy of the methodology leading to the isolation and characterization of these nucleoside analogues.
	
	In this video article, we present a detailed protocol for the synthesis of these modified analogues using phosphorous(III)-based reagents. In addition, the procedure for their biochemical characterization is divulged, with a special emphasis on primer extension reactions and TdT tailing polymerization. This detailed protocol will be of use for the crafting of modified dNTPs and their further use in chemical biology.

The protocol described herein aims to explain and abridge the numerous obstacles in the way of the intricate route leading to modified nucleoside triphosphates. Consequently, this protocol facilitates both the synthesis of these activated building-blocks and their availability for practical applications.

ヌクレオシド三リン酸 - 合成からの生化学的特徴付けへ

The  traditional strategy for the introduction of chemical functionalities is the  use of solid-phase synthesis by appending suitably modified ...

化学

Synthesis of Ligand-free CdS Nanoparticles within a Sulfur Copolymer Matrix

Aliphatic ligands are typically used during the synthesis of nanoparticles to help mediate their growth in addition to operating as high-temperature solvents. These coordinating ligands help solubilize and stabilize the nanoparticles while in solution, and can influence the resulting size and reactivity of the nanoparticles during their formation. Despite the ubiquity of using ligands during synthesis, the presence of aliphatic ligands on the nanoparticle surface can result in a number of problems during the end use of the nanoparticles, necessitating further ligand stripping or ligand exchange procedures. We have developed a way to synthesize cadmium sulfide (CdS) nanoparticles using a unique sulfur copolymer. This sulfur copolymer is primarily composed of elemental sulfur, which is a cheap and abundant material. The sulfur copolymer has the advantages of operating both as a high temperature solvent and as a sulfur source, which can react with a cadmium precursor during nanoparticle synthesis, resulting in the generation of ligand free CdS. During the reaction, only some of the copolymer is consumed to produce CdS, while the rest remains in the polymeric state, thereby producing a nanocomposite material. Once the reaction is finished, the copolymer stabilizes the nanoparticles within a solid polymeric matrix. The copolymer can then be removed before the nanoparticles are used, which produces nanoparticles that do not have organic coordinating ligands. This nascent synthesis technique presents a method to produce metal-sulfide nanoparticles for a wide variety of applications where the presence of organic ligands is not desired.

Herein we present a method to synthesize ligand-free cadmium sulfide (CdS) nanoparticles based on a unique sulfur copolymer. The sulfur copolymer operates as a high temperature solvent and a sulfur source during the nanoparticle synthesis and stabilizes the nanoparticles after the reaction.

硫黄コポリマーマトリックス内リガンドフリーのCdSナノ粒子の合成

Aliphatic ligands are typically used during the synthesis of nanoparticles to help mediate their growth in addition to operating as high-temperature ...

Anionic Polymerization of an Amphiphilic Copolymer for Preparation of Block Copolymer Micelles Stabilized by &#960;-&#960; Stacking Interactions

In this study, an amphiphilic copolymer that includes a core-forming block with phenyl groups was synthesized by living anionic polymerization of phenyl glycidyl ether (PheGE) on methoxy-polyethylene glycol (mPEG-b-PPheGE). Characterization of the copolymer revealed a narrow molecular distribution (PDI &#60; 1.03) and confirmed the degree of polymerization of mPEG122-b-(PheGE)15. The critical micelle concentration of the copolymer was evaluated using an established fluorescence method with the aggregation behavior evaluated by dynamic light scattering and transmission electronic microscopy. The potential of the copolymer for use in drug delivery applications was evaluated in a preliminary manner including in vitro biocompatibility, loading and release of the hydrophobic anti-cancer drug doxorubicin (DOX). A stable micelle formulation of DOX was prepared with drug loading levels up to 14% (wt%), drug loading efficiencies &#62; 60% (w/w) and sustained release of drug over 4 days under physiologically relevant conditions (acidic and neutral pH, presence of albumin). The high drug loading level and sustained release is attributed to stabilizing &#960;-&#960; interactions between DOX and the core-forming block of the micelles.

Anionic Polymerization of an Amphiphilic Copolymer for Preparation of Block Copolymer Micelles Stabilized by &amp;#960;-&amp;#960; Stacking Interactions

The key steps of living anionic polymerization of phenyl glycidyl ether (PheGE) on methoxy-polyethylene glycol (mPEG-b-PPheGE) are described. The resulting block copolymer micelles (BCMs) were loaded with doxorubicin 14% (wt%) and sustained release of drug over 4 days under physiologically relevant conditions was obtained.

π-πスタッキング相互作用によって安定化されたブロック共重合体ミセルの調製のための両親媒性共重合体のアニオン重合

In this study, an amphiphilic copolymer that includes a core-forming block with phenyl groups was synthesized by living anionic polymerization of phenyl ...

Facet-to-facet Linking of Shape-anisotropic Colloidal Cadmium Chalcogenide Nanostructures

Here, we describe a protocol that allows for shape-anisotropic cadmium chalcogenide nanocrystals (NCs), such as nanorods (NRs) and tetrapods (TPs), to be covalently and site-specifically linked via their end facets, resulting in polymer-like linear or branched chains. The linking procedure begins with a cation-exchange process in which the end facets of the cadmium chalcogenide NCs are first converted to silver chalcogenide. This is followed by the selective removal of ligands at their surface. This results in cadmium chalcogenide NCs with highly reactive silver chalcogenide end facets that spontaneously fuse upon contact with each other, thereby establishing an interparticle facet-to-facet attachment. Through the judicious choice of precursor concentrations, an extensive network of linked NCs can be produced. Structural characterization of the linked NCs is carried out via low- and high-resolution transmission electron microscopy (TEM), as well as energy-dispersive X-ray spectroscopy, which confirm the presence of silver chalcogenide domains between chains of cadmium chalcogenide NCs.

A protocol detailing how shape-anisotropic colloidal cadmium chalcogenide nanocrystals can be covalently linked via their end facets is presented here.

ファセットとファセットの形状異方性のコロイド カドミウム カルコゲナイド系ナノ構造のリンク

Here, we describe a protocol that allows for shape-anisotropic cadmium chalcogenide nanocrystals (NCs), such as nanorods (NRs) and tetrapods (TPs), to be ...

Synthesis of Platinum-nickel Nanowires and Optimization for Oxygen Reduction Performance

Platinum-nickel (Pt-Ni) nanowires were developed as fuel cell electrocatalysts, and were optimized for the performance and durability in the oxygen reduction reaction. Spontaneous galvanic displacement was used to deposit Pt layers onto Ni nanowire substrates. The synthesis approach produced catalysts with high specific activities and high Pt surface areas. Hydrogen annealing improved Pt and Ni mixing and specific activity. Acid leaching was used to preferentially remove Ni near the nanowire surface, and oxygen annealing was used to stabilize near-surface Ni, improving durability and minimizing Ni dissolution. These protocols detail the optimization of each post-synthesis processing step, including hydrogen annealing to 250 &#176;C, exposure to 0.1 M nitric acid, and oxygen annealing to 175 &#176;C. Through these steps, Pt-Ni nanowires produced increased activities more than an order of magnitude than Pt nanoparticles, while offering significant durability improvements. The presented protocols are based on Pt-Ni systems in the development of fuel cell catalysts. These techniques have also been used for a variety of metal combinations, and can be applied to develop catalysts for a number of electrochemical processes.

&#160; The protocol describes the synthesis and electrochemical testing of platinum-nickel nanowires. Nanowires were synthesized by the galvanic displacement of a nickel nanowire template. Post-synthesis processing, including hydrogen annealing, acid leaching, and oxygen annealing were used to optimize nanowire performance and durability in the oxygen reduction reaction.

ナノワイヤーの合成プラチナ ニッケルと酸素還元性能の最適化

Platinum-nickel (Pt-Ni) nanowires were developed as fuel cell electrocatalysts, and were optimized for the performance and durability in the oxygen ...

Chemical Precipitation Method for the Synthesis of Nb2O5 Modified Bulk Nickel Catalysts with High Specific Surface Area

We demonstrate a method for the synthesis of NixNb1-xO catalysts with sponge-like and fold-like nanostructures. By varying the Nb:Ni ratio, a series of NixNb1-xO nanoparticles with different atomic compositions (x = 0.03, 0.08, 0.15, and 0.20) have been prepared by chemical precipitation. These NixNb1-xO catalysts are characterized by X-ray diffraction, X-ray photoelectron spectroscopy, and scanning electron microscopy. The study revealed the sponge-like and fold-like appearance of Ni0.97Nb0.03O and Ni0.92Nb0.08O on the NiO surface, and the larger surface area of these NixNb1-xO catalysts, compared with the bulk NiO. Maximum surface area of 173 m2/g can be obtained for Ni0.92Nb0.08O catalysts. In addition, the catalytic hydroconversion of lignin-derived compounds using the synthesized Ni0.92Nb0.08O catalysts have been investigated.

Chemical Precipitation Method for the Synthesis of Nb2O5 Modified Bulk Nickel Catalysts with High Specific Surface Area

A protocol for the synthesis of sponge-like and fold-like Ni1-xNbxO nanoparticles by chemical precipitation is presented.

Nb2O5の合成化学沈殿法変更高表面積一括ニッケル触媒

We demonstrate a method for the synthesis of NixNb1-xO catalysts with sponge-like and fold-like nanostructures. By varying the Nb:Ni ratio, a series of ...

Preparation and Characterization of C60/Graphene Hybrid Nanostructures

Physical thermal deposition in a high vacuum environment is a clean and controllable method for fabricating novel molecular nanostructures on graphene. We present methods for depositing and passively manipulating C60 molecules on rippled graphene that advance the pursuit of realizing applications involving 1D C60/graphene hybrid structures. The techniques applied in this exposition are geared towards high vacuum systems with preparation areas capable of supporting molecular deposition as well as thermal annealing of the samples. We focus on C60 deposition at low pressure using a homemade Knudsen cell connected to a scanning tunneling microscopy (STM) system. The number of molecules deposited is regulated by controlling the temperature of the Knudsen cell and the deposition time. One-dimensional (1D) C60 chain structures with widths of two to three molecules can be prepared via tuning of the experimental conditions. The surface mobility of the C60 molecules increases with annealing temperature allowing them to move within the periodic potential of the rippled graphene. Using this mechanism, it is possible to control the transition of 1D C60 chain structures to a hexagonal close packed quasi-1D stripe structure.

Preparation and Characterization of C60/Graphene Hybrid Nanostructures

Here we present a protocol for the fabrication of C60/graphene hybrid nanostructures by physical thermal evaporation. Particularly, the proper manipulation of deposition and annealing conditions allow the control over the creation of 1D and quasi 1D C60 structures on rippled graphene.

C60/Graphene ハイブリッド ナノ構造の作製と評価

Physical thermal deposition in a high vacuum environment is a clean and controllable method for fabricating novel molecular nanostructures on graphene. We ...

Disentangling High Strength Copolymer Aramid Fibers to Enable the Determination of Their Mechanical Properties

Traditionally, soft body armor has been made from poly(p-phenylene terephthalamide) (PPTA) and ultra-high molecular weight polyethylene. However, to diversify the fiber choices in the United States body armor market, copolymer fibers based on the combination of 5-amino-2-(p-aminophenyl) benzimidazole (PBIA) and the more conventional PPTA were introduced. Little is known regarding the long-term stability of these fibers, but as condensation polymers, they are expected to have potential sensitivity to moisture and humidity. Therefore, characterizing the strength of the materials and understanding their vulnerability to environmental conditions is important for evaluating their use lifetime in safety applications. Ballistic resistance and other critical structural properties of these fibers are predicated on their strength. To accurately determine the strength of the individual fibers, it is necessary to disentangle them from the yarn without introducing any damage. Three aramid-based copolymer fibers were selected for the study. The fibers were washed with acetone followed by methanol to remove an organic coating that held the individual fibers in each yarn bundle together. This coating makes it difficult to separate single fibers from the yarn bundle for mechanical testing without damaging the fibers and affecting their strength. After washing, fourier transform infrared (FTIR) spectroscopy was performed on both washed and unwashed samples and the results were compared. This experiment has shown that there are no significant variations in the spectra of poly(p-phenylene-benzimidazole-terephthalamide-co-p-phenylene terephthalamide) (PBIA-co-PPTA1) and PBIA-co-PPTA3 after washing, and only a small variation in intensity for PBIA. This indicates that the acetone and methanol rinses are not adversely affecting the fibers and causing chemical degradation. Additionally, single fiber tensile testing was performed on the washed fibers to characterize their initial tensile strength and strain to failure, and compare those to other reported values. Iterative procedural development was necessary to find a successful method for performing tensile testing on these fibers.

The primary goal of the study is to develop a protocol to prepare consistent specimens for accurate mechanical testing of high strength copolymer aramid fibers, by removing a coating and disentangling the individual fiber strands without introducing significant chemical or physical degradation.

その力学的特性の測定を可能にする高強度共重合体のアラミド繊維を disentangling

Traditionally, soft body armor has been made from poly(p-phenylene terephthalamide) (PPTA) and ultra-high molecular weight polyethylene. However, to ...

Stable DNA Motifs, 1D and 2D Nanostructures Constructed from Small Circular DNA Molecules

This article presents a detailed protocol for synthesis of small circular DNA molecules, annealing of circular DNA motifs, and construction of 1D and 2D DNA nanostructures. Over decades, the rapid development of DNA nanotechnology is attributed to the use of linear DNAs as the source materials. For example, the DAO (double crossover, antiparallel, odd half-turns) tile is well-known as a building block for construction of 2D DNA lattices; the core structure of DAO is made from two linear single-stranded (ss) oligonucleotides, like two ropes making a right hand granny&#160;knot. Herein, a new type of DNA tiles called cDAO (coupled DAO) are built using a small circular ss-DNA of c64nt or c84nt (circular 64 or 84 nucleotides) as the scaffold strand and several linear ss-DNAs as the staple strands. Perfect 1D and 2D nanostructures are assembled from cDAO tiles: infinite nanowires, nanospirals, nanotubes, nanoribbons; and finite nano-rectangles. Detailed protocols are described: 1) preparation by T4 ligase and purification by denaturing PAGE (polyacrylamide gel electrophoresis) of small circular oligonucleotides, 2) annealing of stable circular tiles, followed by native PAGE analysis, 3) assembling of infinite 1D nanowires, nanorings, nanospirals, infinite 2D lattices of nanotubes and nanoribbons, and finite 2D nano-rectangles, followed by AFM (Atomic Force Microscopy) imaging. The method is simple, robust, and affordable for most labs.

This article presents a detailed protocol for T4 ligation and denaturing PAGE purification of small circular DNA molecules, annealing and native PAGE analysis of circular tiles, assembling and AFM imaging of 1D and 2D DNA nanostructures, as well as agarose gel electrophoresis and centrifugation purification of finite DNA nanostructures.

ナノ構造構築小さな環状 DNA 分子から安定した DNA モチーフ、1 D および 2 D

This article presents a detailed protocol for synthesis of small circular DNA molecules, annealing of circular DNA motifs, and construction of 1D and 2D ...

Gene-therapy Inspired Polycation Coating for Protection of DNA Origami Nanostructures

DNA origami nanostructures hold an immense potential to be used for biological and medical applications. However, low-salt conditions and nucleases in physiological fluids induce denaturation and degradation of self-assembled DNA nanostructures. In non-viral gene delivery, enzymatic degradation of DNA is overcome by the encapsulation of the negatively charged DNA in a cationic shell. Herein, inspired by gene delivery advancements, a simple, one-step and robust methodology is presented for the stabilization of DNA origami nanostructures by coating them with chitosan and linear polyethyleneimine. The polycation coating efficiently protects DNA origami nanostructures in Mg-depleted and nuclease-rich media. This method also preserves the full addressability of enzyme- and aptamer-based functionalization of DNA nanostructures.

Here, a protocol for the protection of DNA origami nanostructures in Mg-depleted and nuclease-rich media using natural cationic polysaccharide chitosan and synthetic linear polyethyleneimine (LPEI) coatings is presented.

遺伝子療法ポリカチオン コーティングに影響を与えた DNA 折り紙ナノ構造体の保護

DNA origami nanostructures hold an immense potential to be used for biological and medical applications. However, low-salt conditions and nucleases in ...