复旦大学：《纳米线材料和功能器件》课程教学资料_纳米线的组装_Directed Assembly of One-Dimensional Nanostructures into Functional Networks

REPORTS ous approaches can now be described as 13. O. Albert, C.A. Gautier, J. C Loulergue, ]. Etchepare, 229(1973). Data for n in the lows In Fig. 4, A and C, the angle between t available at temperatures above 90 not its magnitude. In the absence of dispersion, 15. G. P. wiederrecht et al., Phys. Rev. B 51, 916(1995). and the value of n at the gap[B this leads to a shock-wave singularity because 16. H P. Perry, T..DoughteryPhysRev.8.5778 frared Phys. 23, 359(1983). The latter was used an adjustable parameter to fit the time-domain data of the constructive interference of waves of 17. R.M. Koehl, s. Adachi, K. A Nelson, J. Chem. Phys. 24. T. E. Stevens, thesis, University of Michigan,Ann arbitrary g In Fig 4B, both the angle and q are predetermined because the components of q 18. The calculations were performed with MATH- 25. M. Born, K Huang Dynamical Theory of Crystal Lat- orthogonal to e, are set by the grating. These MATICA Version 4.0(Wolfram Research, Inc, Cham- 26. We used heterodyne detection methods. The pump considerations apply to the imaging experi- hes differ in that e=o outside the a ments of(17)and to early work on polariton for the superluminal case, whereas, for v co, the propagation(27) where the direction of motion tensity does not vanish notwithstanding a substan- with a polarizing beam cube and spect can be identified with that of the Cherenkov (24). The probe beam and a refere ispersed by the spectrometer, were focu ression. Finally, consider single-pump exci tation when the source lateral dimensions are ane)at v co contradicts the phase-velocity argu- ured with a dual channel EG&G 5 sufficiently large that the wave vectors of the er to get△T nent predicting ec= 0 because c/nv can be arDl- 27. G M. Gale, F Vallee, C. Flytzanis, Phys. Rev. Lett. 57. pump pulse and the polariton are nearly col linear. In this case, the phase-matching condi- no). the Cherenkov angle for v co goes all the wi /2 atv= 0. Also note that de/dn oc at eling grating were interpreted in terms of Because q s n2/co at low frequencies, it is clear hich, according to Eq. 4. avoided mode crossings and anharmonic 0. Hence, at subluminal speeds, radiation at these that Cherenkov field profiles can be fairly that phase matching can only be attained at ed, there may be a need to compare the expe subluminal speeds, in agreement 6: see 21. See, e.g. Y.R.Shen, The Principles of Nonlin Fig. 2C. Under the same(quasi-planar) condi- (Wiley, New York, 1984). Materials with 29. V. P. Zrelov, J. Ruzicka, A. A. Tyapkin, JuNR Rapid ons, and not too far from the pump pulse, the field for the grating method results from the density become interference between two polaritons at, say,qx E+Rim)Q). where Eg and Mare electric C. Aku-Leh for assistance with the = +2m/t and q =0, where t is the grating mponents of the pump pulse and that of the alculations and to D G. Steel for critical reading of spacing(12-17). This and Eq. 7 give qt the manuscript. T.E.S. would like to thank the Planck-Institut fur Festkorpertorschung for warm sing (2- vo)). This field is represented in Fig. 22. a ui. 4. Phys. Chem. Ref Data 13, 102(1984) bR928yp四ym 4B by the rectangle with the checkerboard pat asearch under contract F49620-00-1-0328 ten(28) through the Multidisciplinary University Re (22)and at 2 K A GobeL, T Ruf, ]. M. Zhang, RLau tiative program. M Cardona, Phys. Rev. B 59, 2749(1999): T. Hattori, Y. Homma, A. Mitsuishi, M. Tacke, Opt. Commun. 7. 29 September 2000: accepted 30 November 2000 1. v. P. Zrelow Radiation in High-Energy 2. T. Ypsilantis, ]. Seguinot, Nucl. Instrum. Methods A Directed Assembly of 433 3. P. A. Cherenkov. DokL. Akad. Nauk SSSR 2. 451 (1934) One-Dimensional Nanostructures 4. S Vavilov, Dokl. Akad. Nauk SSSR 2, 457(1934). 5. L Frank, Vavilov-Cherenkov Radiation(Nauka, Mos into Functional Networks cow,1988 L Tamm, Dokl Akad. Nauk SSSR 14, 109 Yu Huang, *Xiangfeng Duan, Qingqiao Wei, 7. Expressions for the Cherenkov field in dispersive m dia were first derived by L. Tamm [ Phys. 1. 42 Charles M. Lieber,2+ (1939)and independently by E Fermi(Phys. Rev. 57. 485(1940), who used the Lorentz(single-pole)ap- One-dimensional nanostructures, such as nanowires and nanotubes, represent reduction in the energy loss, a phenomenon kr the smallest dimension for efficient transport of electrons and excitons and thus the density effect. Ignoring dissipation, the are ideal building blocks for hierarchical assembly of functional nanoscale tion for Chere electronic and photonic structures. We report an approach for the hierarchical nance, a partide can in principle radiate at ssembly of one-dimensional nanostructures into well-defined functional net works. We show that nanowires can be assembled into parallel arrays with G. N. Afanasiev, V. G. Kartavenko, E. N. Magar control of the average separation and, by combining fluidic alignment with surface-patterning techniques, that it is also possible to control periodicity In ork was motivated in part by recent CI addition, complex crossed nanowire arrays can be prepared with layer-by-layer 9. To the best of our knowledge, the nume assembly with different flow directions for sequential steps. Transport studies st to uncover diffe show that the crossed nanowire arrays form electrically conducting networks, with individually addressable device function at each cross point. surfaces at which the field exhibits may 10. D. H. Auston, K. P. Cheung, J. A. Valdmanis, D. A Nanoscale materials, for example, nanoclus- rication (1-4). Research focused on zero- Phys. Rev. Leti 65(1984), and ref ters and nanowires(NWs), represent attrac- dimensional nanoclusters has led to substan- tive building blocks for hierarchical assembly tial advances, including the assembly of ar 11. D. A Kleinman, D H. Auston, IEEE J. tron.QE20,964(1984 of functional nanoscale devices that could rays with order extending from nanometer to 12. P. Grenier, D Houde, S JandL, L A Boatner, Phys overcome fundamental and economic limita- micrometer length scales(4-9). In contrast, B50.16295(1994) tions of conventional lithography-based fab- the assembly of one-dimensional (ID)nano- 630 26JanUary2001Vol291ScieNcewww.sciencemag.org

ous approaches can now be described as fol￾lows. In Fig. 4, A and C, the angle between the polariton wave vector and the z axis is fixed, but not its magnitude. In the absence of dispersion, this leads to a shock-wave singularity because of the constructive interference of waves of arbitrary q. In Fig. 4B, both the angle and q are predetermined because the components of q orthogonal to ez are set by the grating. These considerations apply to the imaging experi￾ments of (17) and to early work on polariton propagation (27) where the direction of motion can be identified with that of the Cherenkov expression. Finally, consider single-pump exci￾tation when the source lateral dimensions are sufficiently large that the wave vectors of the pump pulse and the polariton are nearly col￾linear. In this case, the phase-matching condi￾tion is q ' V[n(vL) 1 vLn˙(vL)]/c [ V/cg (vL). Because q ' V/c0 at low frequencies, it is clear that phase matching can only be attained at subluminal speeds, in agreement with Eq. 6; see Fig. 2C. Under the same (quasi-planar) condi￾tions, and not too far from the pump pulse, the field for the grating method results from the interference between two polaritons at, say, qx 5 62p/, and qy 5 0, where , is the grating spacing (12–17). This and Eq. 7 give qz , 5 2p(n2 v2 /c2 2 1)21/2, leading to E ; sin(2px/,) sin[qz (z 2 vt)]. This field is represented in Fig. 4B by the rectangle with the checkerboard pat￾tern (28). References and Notes 1. V. P. Zrelov, Cherenkov Radiation in High-Energy Physics (Israel Program for Scientific Translations, Jerusalem, 1970). 2. T. Ypsilantis, J. Seguinot, Nucl. Instrum. Methods A 433, 1 (1999), and references therein. 3. P. A. Cherenkov, Dokl. Akad. Nauk SSSR 2, 451 (1934). 4. S. Vavilov, Dokl. Akad. Nauk SSSR 2, 457 (1934). 5. I. Frank, Vavilov-Cherenkov Radiation (Nauka, Mos￾cow, 1988). 6. iiii, I. Tamm, Dokl. Akad. Nauk SSSR 14, 109 (1937). 7. Expressions for the Cherenkov field in dispersive me￾dia were first derived by I. Tamm [ J. Phys. 1, 439 (1939)] and independently by E. Fermi [Phys. Rev. 57, 485 (1940)], who used the Lorentz (single-pole) ap￾proximation to show that polarization effects lead to a reduction in the energy loss, a phenomenon known as the density effect. Ignoring dissipation, the condi￾tion for Cherenkov emission reads v 2 . c 2/«(V). Because «(V) can reach large values in the proximity of a resonance, a particle can in principle radiate at arbitrarily small velocities. 8. G. N. Afanasiev, V. G. Kartavenko, E. N. Magar, Physica B 269, 95 (1999), and references therein. This work was motivated in part by recent CR experiments with CERN’s high-energy beam of lead ions (29, 30). 9. To the best of our knowledge, the numerical study of Afanasiev et al. (8) was the first to uncover differences between superluminal and subluminal CR. In their work, these differences manifest themselves in the separate open (v . c0) and closed (v , c0) behavior of the surfaces at which the field exhibits maxima. 10. D. H. Auston, K. P. Cheung, J. A. Valdmanis, D. A. Kleinman, Phys. Rev. Lett. 53, 1555 (1984), and ref￾erences therein. 11. D. A. Kleinman, D. H. Auston, IEEE J. Quantum Elec￾tron. QE-20, 964 (1984). 12. P. Grenier, D. Houde, S. Jandl, L. A. Boatner, Phys. Rev. B 50, 16295 (1994). 13. O. Albert, C. A. Gautier, J. C. Loulergue, J. Etchepare, Solid State Commun. 107, 567 (1998). 14. H. J. Bakker, S. Hunsche, H. Kurz, Rev. Mod. Phys. 70, 523 (1998), and references therein. 15. G. P. Wiederrecht et al., Phys. Rev. B 51, 916 (1995). 16. H. P. Perry, T. P. Doughtery, Phys. Rev. B 55, 5778 (1997). 17. R. M. Koehl, S. Adachi, K. A. Nelson, J. Chem. Phys. 110, 1317 (1999). 18. The calculations were performed with MATH￾EMATICA Version 4.0 (Wolfram Research, Inc., Cham￾paign, IL, 1999). 19. The two regimes differ in that E § 0 outside the cone for the superluminal case, whereas, for v , c0, the intensity does not vanish notwithstanding a substan￾tial drop at the boundary. Hence, there is a shock￾wave singularity at superluminal but not at sublumi￾nal speeds. The presence of a cone (as opposed to a plane) at v , c0 contradicts the phase-velocity argu￾ment predicting uC 5 0 because c/nv can be arbi￾trarily close to unity. 20. Unlike the superluminal case, in which uC # cos21(1/ n0), the Cherenkov angle for v , c0 goes all the way to uC 5 p/2 at v 5 0. Also note that d«/dV 3 ` at V5VC, V0, which, according to Eq. 4, leads to a 5 0. Hence, at subluminal speeds, radiation at these frequencies is concentrated at r 5 0. 21. See, e.g., Y. R. Shen, The Principles of Nonlinear Optics (Wiley, New York, 1984). Materials with infrared￾active vibrations, such as ZnSe, show an additional contribution to the nonlinear polarization due to the combined phonon-photon character of the eigen￾modes. The energy density becomes 2 S%i %k (xikm (2) Em 1 Rik (m) Qm), where %K and Em are electric field components of the pump pulse and that of the infrared radiation, Qm is the amplitude of a phonon component, and R(m) is its associated Raman tensor. 22. H. Li, J. Phys. Chem. Ref. Data 13, 102 (1984). 23. Values of the infrared constants of ZnSe from the literature exhibit considerable scattering. Those in Fig. 2 were interpolated from measurements at 80 K (22) and at 2 K [A. Go¨bel, T. Ruf, J. M. Zhang, R. Lauck, M. Cardona, Phys. Rev. B 59, 2749 (1999); T. Hattori, Y. Homma, A. Mitsuishi, M. Tacke, Opt. Commun. 7, 229 (1973)]. Data for n in the visible range are available at temperatures above 90 K (22). Values at 10 K were obtained from an expression giving n(V) in terms of the band gap, the carrier effective masses, and the value of n at the gap [B. Jensen, A. Torabi, Infrared Phys. 23, 359 (1983)]. The latter was used as an adjustable parameter to fit the time-domain data. 24. T. E. Stevens, thesis, University of Michigan, Ann Arbor (2000). 25. M. Born, K. Huang, Dynamical Theory of Crystal Lat￾tices (Clarendon, Oxford, 1996), p. 100. 26. We used heterodyne detection methods. The pump beam was modulated with a mechanical chopper at 3.51 kHz. The transmitted probe light was analyzed with a polarizing beam cube and spectrally resolved (24). The probe beam and a reference beam, also dispersed by the spectrometer, were focused onto separate photodiodes, and their voltage difference was measured with a dual channel EG&G 5320 digital lock-in amplifier to get DT. 27. G. M. Gale, F. Valle´e, C. Flytzanis, Phys. Rev. Lett. 57, 1867 (1986). 28. In (14), pump-probe data for polaritons generated with a traveling grating were interpreted in terms of avoided mode crossings and anharmonicity. Given that Cherenkov field profiles can be fairly complicat￾ed, there may be a need to compare the experiments with calculations of the field due to a finite traveling grating before such interpretations can be accepted. 29. V. P. Zrelov, J. Ruzicka, A. A. Tyapkin, JINR Rapid Commun. 1[87]-98, 23 (1998). 30. V. P. Zrelor, J. Ruzicka, A. A. Tyapkin, CERN Courier 38 (no. 9), 7 (1998)]. 31. We are grateful to C. Aku-Leh for assistance with the calculations and to D. G. Steel for critical reading of the manuscript. T.E.S. would like to thank the Max￾Planck-Institut fu¨r Festko¨rpertorschung for warm hospitality. Work supported by the NSF under grant DMR 9876862 and by the Air Force Office of Scien￾tific Research under contract F49620-00-1-0328 through the Multidisciplinary University Research Ini￾tiative program. 29 September 2000; accepted 30 November 2000 Directed Assembly of One-Dimensional Nanostructures into Functional Networks Yu Huang,1 * Xiangfeng Duan,1 * Qingqiao Wei,1 Charles M. Lieber1,2† One-dimensional nanostructures, such as nanowires and nanotubes, represent the smallest dimension for efficient transport of electrons and excitons and thus are ideal building blocks for hierarchical assembly of functional nanoscale electronic and photonic structures. We report an approach for the hierarchical assembly of one-dimensional nanostructures into well-defined functional net￾works. We show that nanowires can be assembled into parallel arrays with control of the average separation and, by combining fluidic alignment with surface-patterning techniques, that it is also possible to control periodicity. In addition, complex crossed nanowire arrays can be prepared with layer-by-layer assembly with different flow directions for sequential steps. Transport studies show that the crossed nanowire arrays form electrically conducting networks, with individually addressable device function at each cross point. Nanoscale materials, for example, nanoclus￾ters and nanowires (NWs), represent attrac￾tive building blocks for hierarchical assembly of functional nanoscale devices that could overcome fundamental and economic limita￾tions of conventional lithography-based fab￾rication (1–4). Research focused on zero￾dimensional nanoclusters has led to substan￾tial advances, including the assembly of ar￾rays with order extending from nanometer to micrometer length scales (4–9). In contrast, the assembly of one-dimensional (1D) nano￾R EPORTS 630 26 JANUARY 2001 VOL 291 SCIENCE www.sciencemag.org

REPORTS structures, such as NWs and carbon nano- alignment and average separation of the direction (inset, Fig. 2C). Our observed bes (nts), has met with much less success NWs. First, we find that the degree of align- results can be explained within the frame- (10-12), although these materials offer great ment can be controlled by the flow rate. With work of shear flow(21, 22). Specifically, the potential as building blocks for applications increasing flow rates, the width of the Nw channel flow near the substrate surface re- in nanoelectronics (1-3, 13-16)and photon- angular distribution with respect to the flow sembles a shear flow and aligns the Nws in direction(e.g, inset in Fig. 2C) substantially the flow direction before they are immobi- To achieve the substantial potential of narrows. Comparison of the distribution lized on the substrate. Higher flow rates pro- NWs and NTs in these and other areas of widths measured over a range of conditions duce larger shear forces and hence lead to nanotechnology will require the controlled shows that the width decreases quickly from better alignment. and predictable assembly of well-ordered our lowest flow rate, 4 mm/s, and ap. In addition, the average Nw surface cov- structures. We report an approach for the proaches a nearly constant value at 10 erage can be controlled by the flow duration hierarchical assembly of ID nanostructures mm/s(Fig. 2C). At the highest flow rates(Fig 2D). Experiments carried out at a con- whereby NWs are aligned in fluid flows with examined in our studies, more than 80% of stant flow rate show that the Nw density the separation and spatial location readily the NWs are aligned within +5 of the flow increases systematically with flow duration. ontrolled. Crossed Nw arrays were also pre. pared with layer-by-layer assembly with dif- Fig. 1. Schematic of fluidic A ferent flow directions for sequential steps. nnel structures for flow as- o-s=Q Transport studies show that the crossed Nw sembly. (A)A channel formed arrays form electrically conducting networks, when the PDMS mold was PDMS mold with individually addressable device function substrate. Nw assembly was at each NW-NW cross point. This approach carried out by flowing an Nw ubstrate can be potentially used for organizing other care 9 olled flow rate for a de the channel B arallel array ID nanostructures into highly integrated de- with vice arrays and thus offers a general pathway set duration. Parallel arrays of for bottom-up assembly of new electronic NWs are observed in the flow and photonic nanosystems. direction on the substrate The gallium phosphide (GaP), indium when the PDMS mold is re- phosphide(InP), and silicon(Si)NWs used Nw arrays can be obtained in these studies were synthesized by laser- by changing the flow direc- ssisted catalytic growth(1, 18, 19)and sub- tion sec tially in a laye first laver crossed array quently suspended in ethanol solution. In by-layer assembly process general, we assembled arrays of NWs by passing suspensions of the NWs through flu idic channel structures formed between a B poly(dimethylsiloxane)(PDMS) mold(20) and a flat substrate(Fig. 1). Parallel and crossed arrays of NWs can be readily achieved with single(Fig. 1A)and sequentia crossed(Fig. 1B)flows, respectively, for the assembly process as described below. a typical example of parallel assembly of NWs(Fig. 2A) shows that virtually all the NWs are aligned along one direction, i.e., the flow direction. There are also some small 16Fc deviations with respect to the flow direction, 250}D which we will discuss below Examination of 三200 the assembled (Fig. 2B) shows that the alignment readily ≥150 10 extends over hundreds of micrometers. In d, alignment of the Nws has been found 目 ▲Ange(deg) to extend up to millimeter length scales and seems to be limited by the size of the fluidic channels, on the basis of experiments carried out with channels with widths ranging from Flow rate(mm/s) 010203040 50 to 500 um and lengths from 6 to 20 mm. We carried out several types of experi- Fig. 2. Parallel assembly of NW arrays (A and B)SEM images of parallel arrays of InP NWs aligned ments to understand factors controlling the by channel fiow. The scale bars correspond to z m and 5o tim in (A and (B), respectively. The bled monolayer(SAM) by immersion in a 1 mM chloro triethoxysilane(APTES)for 30 min, followed by heating at 110 C for 10 min(10). All of the substrates used in the following experiment were functionalized in a similar way unless otherwise pecified. (C)NW angular spread with respect to the flow direction versus flow rate. Each data hould be addressed. E. The average density of NWs versus flow time. The average density was calculated by dividing the qually to this work. average number of NWs at any cross section of the channel by the width of the channeL All of the mail cml@cmliris. harvard. edu periments were carried out with a flow rate of 6.40 mm/s www.sciencemagorgSciEnceVol29126jAnuAry2001 631

structures, such as NWs and carbon nano￾tubes (NTs), has met with much less success (10–12), although these materials offer great potential as building blocks for applications in nanoelectronics (1–3, 13–16) and photon￾ics (17). To achieve the substantial potential of NWs and NTs in these and other areas of nanotechnology will require the controlled and predictable assembly of well-ordered structures. We report an approach for the hierarchical assembly of 1D nanostructures whereby NWs are aligned in fluid flows with the separation and spatial location readily controlled. Crossed NW arrays were also pre￾pared with layer-by-layer assembly with dif￾ferent flow directions for sequential steps. Transport studies show that the crossed NW arrays form electrically conducting networks, with individually addressable device function at each NW-NW cross point. This approach can be potentially used for organizing other 1D nanostructures into highly integrated de￾vice arrays and thus offers a general pathway for bottom-up assembly of new electronic and photonic nanosystems. The gallium phosphide (GaP), indium phosphide (InP), and silicon (Si) NWs used in these studies were synthesized by laser￾assisted catalytic growth (1, 18, 19) and sub￾sequently suspended in ethanol solution. In general, we assembled arrays of NWs by passing suspensions of the NWs through flu￾idic channel structures formed between a poly(dimethylsiloxane) (PDMS) mold (20) and a flat substrate (Fig. 1). Parallel and crossed arrays of NWs can be readily achieved with single (Fig. 1A) and sequential crossed (Fig. 1B) flows, respectively, for the assembly process as described below. A typical example of parallel assembly of NWs (Fig. 2A) shows that virtually all the NWs are aligned along one direction, i.e., the flow direction. There are also some small deviations with respect to the flow direction, which we will discuss below. Examination of the assembled NWs on larger length scales (Fig. 2B) shows that the alignment readily extends over hundreds of micrometers. In￾deed, alignment of the NWs has been found to extend up to millimeter length scales and seems to be limited by the size of the fluidic channels, on the basis of experiments carried out with channels with widths ranging from 50 to 500 mm and lengths from 6 to 20 mm. We carried out several types of experi￾ments to understand factors controlling the alignment and average separation of the NWs. First, we find that the degree of align￾ment can be controlled by the flow rate. With increasing flow rates, the width of the NW angular distribution with respect to the flow direction (e.g., inset in Fig. 2C) substantially narrows. Comparison of the distribution widths measured over a range of conditions shows that the width decreases quickly from our lowest flow rate, ;4 mm/s, and ap￾proaches a nearly constant value at ;10 mm/s (Fig. 2C). At the highest flow rates examined in our studies, more than 80% of the NWs are aligned within 65° of the flow direction (inset, Fig. 2C). Our observed results can be explained within the frame￾work of shear flow (21, 22). Specifically, the channel flow near the substrate surface re￾sembles a shear flow and aligns the NWs in the flow direction before they are immobi￾lized on the substrate. Higher flow rates pro￾duce larger shear forces and hence lead to better alignment. In addition, the average NW surface cov￾erage can be controlled by the flow duration (Fig. 2D). Experiments carried out at a con￾stant flow rate show that the NW density increases systematically with flow duration. 1 Department of Chemistry and Chemical Biology, Harvard University, Cambridge, MA 02138, USA. 2 Di￾vision of Engineering and Applied Sciences, Harvard University, Cambridge, MA 02138, USA. *These authors contributed equally to this work. †To whom correspondence should be addressed. E￾mail: cml@cmliris.harvard.edu Fig. 1. Schematic of fluidic channel structures for flow as￾sembly. (A) A channel formed when the PDMS mold was brought in contact with a flat substrate. NW assembly was carried out by flowing an NW suspension inside the channel with a controlled flow rate for a set duration. Parallel arrays of NWs are observed in the flow direction on the substrate when the PDMS mold is re￾moved. (B) Multiple crossed NW arrays can be obtained by changing the flow direc￾tion sequentially in a layer￾by-layer assembly process. Fig. 2. Parallel assembly of NW arrays. (A and B) SEM images of parallel arrays of InP NWs aligned by channel flow. The scale bars correspond to 2 mm and 50 mm in (A) and (B), respectively. The silicon (SiO2/Si) substrate used in flow assembly was functionalized with an NH2-terminated self-assembled monolayer (SAM) by immersion in a 1 mM chloroform solution of 3-aminopropyl￾triethoxysilane (APTES) for 30 min, followed by heating at 110°C for 10 min (10). All of the substrates used in the following experiment were functionalized in a similar way unless otherwise specified. (C) NW angular spread with respect to the flow direction versus flow rate. Each data point in the figure was obtained by statistical analysis of angular distribution of ;200 NWs (e.g., see inset). The inset shows a histogram of NW angular distribution at a flow rate of 9.40 mm/s. (D) The average density of NWs versus flow time. The average density was calculated by dividing the average number of NWs at any cross section of the channel by the width of the channel. All of the experiments were carried out with a flow rate of 6.40 mm/s. R EPORTS www.sciencemag.org SCIENCE VOL 291 26 JANUARY 2001 631

REP。RTs In these experiments, a flow duration of 30 order of 100 nm or less. We note that the rapidly on NH, terminated monolayers. min produced a density of about 250 Nws deposition rate and hence average separation which have a partial positive charge, than on per 100 um or an average NW-NW separa- versus time depend strongly on the surface either methy l-terminated monolayers or bare tion of -400 nm. Extended deposition time chemical functionality. Specifically, we show SiO, surfaces. It is also important to red can produce NW arrays with spacings on the that the GaP, InP, and Si NWs deposit more nize that the minimum separation of align.i NWs that can be achieved without NW-Nw Assem bly of A contacts will depend on the lengths of the array NWs used in the assembly process. Recent (A)Schematic view of progress demonstrating control of Nw lengths from the 100-nm to tens-of-microme nto a chemically pat- ter scale (23)should increase the terned substrate. The accessible spacings without contact ight gray areas corre- Our results demonstrate ordering of Nw SiO, /Si substrate structure over multiple length scalesorga as the dark gray areas nization of nanometer diameter wires with correspond to either 100-nm to micrometer-scale separations over ethyl-terminated or C millimeter-scale areas. This hierarchical or NWs der can readily bridge the microscopic and terminated 2 macroscopic worlds, although to enable as- sembly with greatest control requires that the atial position also be defined. We achieved Parallel arrays of GaP this important goal by using complementary NWs aligned on poly chemical interactions between chemically patterned substrates and NWs(Fig. 3A) Scanning electron microscopy(SEM) images paration. The dark regions in the of representative experiments( Fig 3, B to D) rrespond to the NH -terminated Sio, /Si surface. The NWs are preferentially attracted to NH ated regions. The PMMA was patterned with standard electron beam(E-beam)lithography, and the same as those of the surface patterns. the resulting SiOz surface was functionalized by immersion in a solution of 0.5% APTES in ethanol for These data demonstrate that the Nws are 10 min, followed by 10 min at 100 C. The scale bars correspond to 5 um and 2 um in(B)and (C). preferentially assembled at positions de pectively.(D)Parallel arrays of GaP NWs with 500-nm separation obtained with a patterned SAM by the chemical patten and, moreover, surface. The sio / Si surface was first functionalized with methy -terminate 0c immersion in pure that the periodic patterns can organize the by functionalization with APTEs y to form an array of parallel features with a 500-nm period, followed NWs into a regular superstructure. It is im termed by e-beam lithe ) The sc ant to recognize that the patterned surface alone does not provide good control of the ID nanostructure organization. Assembly of NTs Fig. 4, Layer-by-layer A (10, I1) and NWs(24) on patterned sub- port measurements of strates shows 1D nanostructures aligned with crossed NW arrays (A bridging, and looping around patterned areas and B)Typical SEM with little directional control. Our use of fluid flows avoids these substantial problems and ays of InP NWs ob- nables controlled assembly in one or more assembly process with directions. By combining this approach with orthogonal flow direc ng method nanoscale domain formation in diblock c tial steps Flow direc-B a polymers(25) and spontaneous ordering of tions are highlighted molecules(26 ), it should by erate well-ordered Nw arrays beyond the ingle of GaP NWs limitations of conventional lithography obtained in a three- Our general approach can be used to or ganize NWs into with60° angles be structures. which are critical for building dense nanodevice arrays, with the use of the which are indicated by layer-by-layer scheme illustrated in Fig. 1B abered arrows The scale bars correspond to 500 nm in E (A),(B), and(C). (D)SEM image of a typical 2 by 2 cross The formation of crossed and more complex ial assembly of n-typ NWs with uctures requires that the nanostructure-sub- rthogonal flows. Ni/in/Au contact electrodes, which we strate interaction is sufficiently strong that posited by thermal evaporation, were patterned by E sequential flow steps do not affect preceding beam lithography. The NWs were briefly(3 to 5 s)etc ones: We find that this condition can be in oxid achieved. For example, alternating the flow layer before electrode deposition. The scale bar corre- sponds to 2 um.(E)Representative l-V curves from two- O in orthogonal directions in a two-step assem- rminal measurements on a 2 by 2 crossed array. the bly process yields crossbar structures(Fig. 4, reen curves represent the i-V of four individual NWs(ad -0.8. 4 0.0 0.4 0.8 A and B). Both figures show that multiple bg, cf, eh), and the red curves represent /-V across the four Voltage(V) crossbars can be obtained with only hundreds n-n crossed junctions(ab, cd, ef, gh) of nanometer separations between individual 632 26JanUary2001Vol291ScieNcewww.sciencemag.org

In these experiments, a flow duration of 30 min produced a density of about 250 NWs per 100 mm or an average NW-NW separa￾tion of ;400 nm. Extended deposition time can produce NW arrays with spacings on the order of 100 nm or less. We note that the deposition rate and hence average separation versus time depend strongly on the surface chemical functionality. Specifically, we show that the GaP, InP, and Si NWs deposit more rapidly on NH2-terminated monolayers, which have a partial positive charge, than on either methyl-terminated monolayers or bare SiO2 surfaces. It is also important to recog￾nize that the minimum separation of aligned NWs that can be achieved without NW-NW contacts will depend on the lengths of the NWs used in the assembly process. Recent progress demonstrating control of NW lengths from the 100-nm to tens-of-microme￾ter scale (23) should increase the range of accessible spacings without contact. Our results demonstrate ordering of NW structure over multiple length scales—orga￾nization of nanometer diameter wires with 100-nm to micrometer-scale separations over millimeter-scale areas. This hierarchical or￾der can readily bridge the microscopic and macroscopic worlds, although to enable as￾sembly with greatest control requires that the spatial position also be defined. We achieved this important goal by using complementary chemical interactions between chemically patterned substrates and NWs (Fig. 3A). Scanning electron microscopy (SEM) images of representative experiments (Fig. 3, B to D) show parallel NW arrays with lateral periods the same as those of the surface patterns. These data demonstrate that the NWs are preferentially assembled at positions defined by the chemical pattern and, moreover, show that the periodic patterns can organize the NWs into a regular superstructure. It is im￾portant to recognize that the patterned surface alone does not provide good control of the 1D nanostructure organization. Assembly of NTs (10, 11) and NWs (24) on patterned sub￾strates shows 1D nanostructures aligned with, bridging, and looping around patterned areas with little directional control. Our use of fluid flows avoids these substantial problems and enables controlled assembly in one or more directions. By combining this approach with other surface-patterning methods, such as nanoscale domain formation in diblock co￾polymers (25) and spontaneous ordering of molecules (26), it should be possible to gen￾erate well-ordered NW arrays beyond the limitations of conventional lithography. Our general approach can be used to or￾ganize NWs into more complex crossed structures, which are critical for building dense nanodevice arrays, with the use of the layer-by-layer scheme illustrated in Fig. 1B. The formation of crossed and more complex structures requires that the nanostructure-sub￾strate interaction is sufficiently strong that sequential flow steps do not affect preceding ones: We find that this condition can be achieved. For example, alternating the flow in orthogonal directions in a two-step assem￾bly process yields crossbar structures (Fig. 4, A and B). Both figures show that multiple crossbars can be obtained with only hundreds of nanometer separations between individual Fig. 3. Assembly of periodic NW arrays. (A) Schematic view of the assembly of NWs onto a chemically pat￾terned substrate. The light gray areas corre￾spond to NH2-termi￾nated surfaces, where￾as the dark gray areas correspond to either methyl-terminated or bare surfaces. NWs are preferentially at￾tracted to the NH2- terminated regions of the surface. (B and C) Parallel arrays of GaP NWs aligned on poly- (methyl methacrylate) (PMMA) patterned sur￾face with 5- and 2-mm separation. The dark regions in the image correspond to residual PMMA, whereas the bright regions correspond to the NH2-terminated SiO2/Si surface. The NWs are preferentially attracted to NH2- terminated regions. The PMMA was patterned with standard electron beam (E-beam) lithography, and the resulting SiO2 surface was functionalized by immersion in a solution of 0.5% APTES in ethanol for 10 min, followed by 10 min at 100°C. The scale bars correspond to 5 mm and 2 mm in (B) and (C), respectively. (D) Parallel arrays of GaP NWs with 500-nm separation obtained with a patterned SAM surface. The SiO2/Si surface was first functionalized with methyl-terminated SAM by immersion in pure hexamethyldisilazane (HMDS) for 15 min at 50°C, followed by 10 min at 110°C. This surface was patterned by E-beam lithography to form an array of parallel features with a 500-nm period, followed by functionalization with APTES (10). The scale bar corresponds to 500 nm. Fig. 4. Layer-by-layer assembly and trans￾port measurements of crossed NW arrays. (A and B) Typical SEM images of crossed ar￾rays of InP NWs ob￾tained in a two-step assembly process with orthogonal flow direc￾tions for the sequen￾tial steps. Flow direc￾tions are highlighted by arrows in the imag￾es. (C) An equilateral triangle of GaP NWs obtained in a three￾step assembly process, with 60° angles be￾tween flow directions, which are indicated by numbered arrows. The scale bars correspond to 500 nm in (A), (B), and (C). (D) SEM image of a typical 2 by 2 cross array made by sequential assembly of n-type InP NWs with orthogonal flows. Ni/In/Au contact electrodes, which were deposited by thermal evaporation, were patterned by E￾beam lithography. The NWs were briefly (3 to 5 s) etched in 6% HF solution to remove the amorphous oxide outer layer before electrode deposition. The scale bar corre￾sponds to 2 mm. (E) Representative I-V curves from two￾terminal measurements on a 2 by 2 crossed array. The green curves represent the I-V of four individual NWs (ad, bg, cf, eh), and the red curves represent I-V across the four n-n crossed junctions (ab, cd, ef, gh). R EPORTS 632 26 JANUARY 2001 VOL 291 SCIENCE www.sciencemag.org

REP。RT5 cross points in a very straightforward, low- LEDs and electronically more complex nano- 7. A K. Boal et al, Nature 404, 746(2000) cost, fast, and scalable process. Although the devices. 8. R. C. Hayward, D. A. Sayille, I. A Aksay, Nature 404, separations between individual NWs are not These studies provide a general and ratio- 9. M. L, H. Schnablegger, s. Mann, Nature 402,393 completely uniform, a periodic array can be nal approach for hierarchical assembly of ll asily envisioned with a patterned surface as nanomaterials into well-defined functional 10. J. Liu et al, Chem. Phys. Lett. 303, 125 11. M. Burghard et al an yield functional devices(see below). We believe that our approach for directed shown that NWs can be assembled into par- 15.T Rueckes et al. Science 289, 94(2000) assembly of multiple crossed NW arrays offers allel arrays with control of the average sepa- 16.X. Duan et al. Nature 409,66(2001) substantial advantages over current efforts, ration and, by combining fluidic alignment 17. S Noda et al, Science 289,604 direct manipulation of individual NWs and NTs also possible to control periodicity. In addi- 19. Y Cu X Duan Hu, C M Lieber, J. Phys. Chem. B (15), and electric fields(12, 16, 27)to make tion, we have demonstrated the possibility of 20. D. C Duffy et al., Anal. Chem. 70, 4974(1998) single crossed structures. With random deposi- layer-by-layer assembly of crossed and more 21. C A Stover, D L Koch, C. Cohen, J. Fluid Mech. 238 tion and manipulation, it is difficult to obtain complex structures by varying the flow direc- 22 D L Koch,ESG Shaqfeh, Phys. Fluids A 2, 2093(1990). ultiple crossbars required for integrated nano- tion in sequential steps and have obtained 23. We have shown that the Nws with well-defined an evices. Although electric fields enable more preliminary results suggesting that this ap- controllable lengths can be prepared using gold nano control over assembly, this method is also lim- proach can be extended to lD nanostructures, ited by O electrostatic interference between such as carbon NTs(28), We believe that 24. Y Hua ng x uan. C M, Lieber, unpublished data nearby electrodes as separations are scaled be- flow assembly represents a general strategy 25. C De Rosa et al, Macromolecules 33, 4871(2000) nent of extensive lithography to fabricate the blocks into structures needed for wiring, in- z7. heCtic felds can be used to align suspensions of emiconductor Nws into parallel Nw arrays ar structures. Our fluidic approach is intrinsically could enable a bottom-up manufacturing par- very parallel and scalable and, moreover, it adigm for future nanotechnologies. trode arrays are used to create a field pa allows for the directed assembly of geometri- tial complications in the assembly of multiple cross References and notes at the submicrometer scale the angles between flow directions in sequential 1.J Hu, T w. Odom, C M Lieber, Acc. Chem. Res 32, 28. Additional studies show that suspensions of single- assembly steps. For example, an equilateral tri- 2. C. Dekker, Phys. Today 52(no 5), 22( 1999) gle(Fig. 4C)was assembled in a three- layer 3. J. R Heath et al. Science 280, 1716(1998) kin, inorg. Chem. 39 deposition sequence with 60 angles between 5. C.B. Murray. C.R. Kagan, M.G.Bawendi, Science 270, acknowledges support of this wor the three flow directions. The method of flow by the Office of Naval Research and Defense vanced Projects Research Agency alignment thus provides a flexible way to meet 6. C P Collier et al, Annu. Rev. Phys. Chem. 49, 371 October 2000: accepted 13 December 2000 tions, including those requiring assembly of multiple"layers"of NWs. An important feature of this layer-by-layer Fast Drop Movements Resulting dent of the others, and thus a variety of homo- and heterojunction configurations can be ob- from the Phase Change on ained at each crossed point by simply changing the composition of the NW suspension used fo Gradient Surface each step. For example, it should be possible to Susan DanieL, Manoj John C che dividual nanoscale devices using our approach with n-type and p-type NWs(16, 19)and NTs, The movement of liquid drops on a surface with a radial surface tension gradient in which the nws and nts act as both the is described here. When saturated steam passes over a colder hydrophobic wiring and active device elements(15). A typ substrate, numerous water droplets nucleate and grow by coalesc ical 2 by 2 crossbar array made of n-type InP surrounding drops. The merging droplets exhibit two-dimensional random mo NWs. in which all eight ends of the Nws tion somewhat like the Brownian movements of colloidal particles. when a urface tension gradient is designed into the substrate surface, the random this point(Fig. 4D). Transport measurements movements of droplets are biased toward the more wettable side of the surface ( Fig. 4E) show that current can flow through Powered by the energies of coalescence and collimated by the forces of the any two of the eight ends and enable the elec- chemical gradient, small drops(0.1 to 0. 3 millimeter) display speeds that are trical characteristics of individual Nws and the hundreds to thousands of times faster than those of typical Marangoni flows NW-NW junctions to be assessed. The current- This effect has implications for passively enhancing heat transfer in heat voltage(1-n data recorded for each of the four changers and heat pipes. cross points exhibit linear or nearly linear be- havior(red curves) and are consistent with ex- The movements of liquids resulting fror analysis devices(2). Although the usual Ma- pectations for n-n type junctions. Because sin- anced surface tension forces constitute rangoni motions are triggered by variations in e Nw-NW p-n junctions formed by random portant surface phenomenon, known as temperature or composition on a liquid surface, deposition exhibit behavior characteristic of rangoni effect (). When regulated properly, a surface tension heterogeneity(5-7)on a solid light-emitting diodes (LEDs)(16), we believe these types of flows are of value in several substrate can also induce such motion. The typ- that our approach could be used to assemble industrial applications, such as the design and ical speeds of these flows(speeds ranging from high-density and individually addressable nano- operation of microfluidic and integrated dNa micrometers to millimeters per second)or encemag org SCIENCE VOL 291 26 JANUARY 2001 633

cross points in a very straightforward, low￾cost, fast, and scalable process. Although the separations between individual NWs are not completely uniform, a periodic array can be easily envisioned with a patterned surface as described above. These crossbar structures can yield functional devices (see below). We believe that our approach for directed assembly of multiple crossed NW arrays offers substantial advantages over current efforts, which have used random deposition (14, 16), direct manipulation of individual NWs and NTs (15), and electric fields (12, 16, 27) to make single crossed structures. With random deposi￾tion and manipulation, it is difficult to obtain multiple crossbars required for integrated nano￾devices. Although electric fields enable more control over assembly, this method is also lim￾ited by (i) electrostatic interference between nearby electrodes as separations are scaled be￾low the micrometer level and (ii) the require￾ment of extensive lithography to fabricate the electrodes for assembly of multiple NW device structures. Our fluidic approach is intrinsically very parallel and scalable and, moreover, it allows for the directed assembly of geometri￾cally complex structures by simply controlling the angles between flow directions in sequential assembly steps. For example, an equilateral tri￾angle (Fig. 4C) was assembled in a three-layer deposition sequence with 60° angles between the three flow directions. The method of flow alignment thus provides a flexible way to meet the requirements of many device configura￾tions, including those requiring assembly of multiple “layers” of NWs. An important feature of this layer-by-layer assembly scheme is that each layer is indepen￾dent of the others, and thus a variety of homo￾and heterojunction configurations can be ob￾tained at each crossed point by simply changing the composition of the NW suspension used for each step. For example, it should be possible to directly assemble and subsequently address in￾dividual nanoscale devices using our approach with n-type and p-type NWs (16, 19) and NTs, in which the NWs and NTs act as both the wiring and active device elements (15). A typ￾ical 2 by 2 crossbar array made of n-type InP NWs, in which all eight ends of the NWs are connected by metal electrodes, demonstrates this point (Fig. 4D). Transport measurements (Fig. 4E) show that current can flow through any two of the eight ends and enable the elec￾trical characteristics of individual NWs and the NW-NW junctions to be assessed. The current￾voltage (I-V) data recorded for each of the four cross points exhibit linear or nearly linear be￾havior (red curves) and are consistent with ex￾pectations for n-n type junctions. Because sin￾gle NW-NW p-n junctions formed by random deposition exhibit behavior characteristic of light-emitting diodes (LEDs) (16), we believe that our approach could be used to assemble high-density and individually addressable nano￾LEDs and electronically more complex nano￾devices. These studies provide a general and ratio￾nal approach for hierarchical assembly of 1D nanomaterials into well-defined functional networks that can bridge the nanometer through millimeter size regimes. We have shown that NWs can be assembled into par￾allel arrays with control of the average sepa￾ration and, by combining fluidic alignment with surface-patterning techniques, that it is also possible to control periodicity. In addi￾tion, we have demonstrated the possibility of layer-by-layer assembly of crossed and more complex structures by varying the flow direc￾tion in sequential steps and have obtained preliminary results suggesting that this ap￾proach can be extended to 1D nanostructures, such as carbon NTs (28). We believe that flow assembly represents a general strategy for organization of NW and NT building blocks into structures needed for wiring, in￾terconnects, and functional devices and thus could enable a bottom-up manufacturing par￾adigm for future nanotechnologies. References and Notes 1. J. Hu, T. W. Odom, C. M. Lieber, Acc. Chem. Res. 32, 435 (1999). 2. C. Dekker, Phys. Today 52 (no. 5), 22 (1999). 3. J. R. Heath et al., Science 280, 1716 (1998). 4. C. A. Mirkin, Inorg. Chem. 39, 2258 (2000). 5. C. B. Murray, C. R. Kagan, M. G. Bawendi, Science 270, 1335 (1995). 6. C. P. Collier et al., Annu. Rev. Phys. Chem. 49, 371 (1998). 7. A. K. Boal et al., Nature 404, 746 (2000). 8. R. C. Hayward, D. A. Sayille, I. A. Aksay, Nature 404, 56 (2000). 9. M. Li, H. Schnablegger, S. Mann, Nature 402, 393 (1999). 10. J. Liu et al., Chem. Phys. Lett. 303, 125 (1999). 11. M. Burghard et al., Adv. Mater. 10, 584 (1998). 12. P. A. Smith et al., Appl. Phys. Lett. 77, 1399 (2000). 13. S. J. Tan et al., Nature 393, 49 (1998). 14. M. S. Fuher et al., Science 288, 494 (2000). 15. T. Rueckes et al., Science 289, 94 (2000). 16. X. Duan et al., Nature 409, 66 (2001). 17. S. Noda et al., Science 289, 604 (2000). 18. X. Duan, C. M. Lieber, Adv. Mater. 12, 298 (2000). 19. Y. Cui, X. Duan, J. Hu, C. M. Lieber, J. Phys. Chem. B 104, 5213 (2000). 20. D. C. Duffy et al., Anal. Chem. 70, 4974 (1998). 21. C. A. Stover, D. L. Koch, C. Cohen, J. Fluid Mech. 238, 277 (1992). 22. D. L. Koch, E. S. G. Shaqfeh, Phys. Fluids A 2, 2093 (1990). 23. We have shown that the NWs with well-defined and controllable lengths can be prepared using gold nano￾cluster catalysts (M. S. Gudiksen, J. Wang, C. M. Lieber, in preparation). 24. Y. Huang, X. Duan, C. M. Lieber, unpublished data. 25. C. De Rosa et al., Macromolecules 33, 4871 (2000). 26. M. Gleiche, L. F. Chi, H. Fuchs, Nature 403, 173 (2000). 27. Electric fields can be used to align suspensions of semiconductor NWs into parallel NW arrays and single NW crosses (16), where patterned microelec￾trode arrays are used to create a field pattern. Fring￾ing fields and charging can, however, lead to substan￾tial complications in the assembly of multiple crosses at the submicrometer scale. 28. Additional studies show that suspensions of single￾walled carbon nanotubes and duplex DNA can be aligned in parallel arrays with the fluidic approach. 29. We thank H. Stone, J. Ng, and T. Rueckes for helpful discussions. C.M.L. acknowledges support of this work by the Office of Naval Research and Defense Ad￾vanced Projects Research Agency. 10 October 2000; accepted 13 December 2000 Fast Drop Movements Resulting from the Phase Change on a Gradient Surface Susan Daniel, Manoj K. Chaudhury,* John C. Chen The movement of liquid drops on a surface with a radial surface tension gradient is described here. When saturated steam passes over a colder hydrophobic substrate, numerous water droplets nucleate and grow by coalescence with the surrounding drops. The merging droplets exhibit two-dimensional random mo￾tion somewhat like the Brownian movements of colloidal particles. When a surface tension gradient is designed into the substrate surface, the random movements of droplets are biased toward the more wettable side of the surface. Powered by the energies of coalescence and collimated by the forces of the chemical gradient, small drops (0.1 to 0.3 millimeter) display speeds that are hundreds to thousands of times faster than those of typical Marangoni flows. This effect has implications for passively enhancing heat transfer in heat ex￾changers and heat pipes. The movements of liquids resulting from unbal￾anced surface tension forces constitute an im￾portant surface phenomenon, known as the Ma￾rangoni effect (1). When regulated properly, these types of flows are of value in several industrial applications, such as the design and operation of microfluidic and integrated DNA analysis devices (2–4). Although the usual Ma￾rangoni motions are triggered by variations in temperature or composition on a liquid surface, a surface tension heterogeneity (5–7) on a solid substrate can also induce such motion. The typ￾ical speeds of these flows (speeds ranging from micrometers to millimeters per second) on a R EPORTS www.sciencemag.org SCIENCE VOL 291 26 JANUARY 2001 633