Oriented Attachment Of Zno Nanocrystals Biology Essay

Self-organization of nanoparticles is a major issue to synthesise mesoscopic constructions. Among the possible mechanisms taking to self-organisation, the orientated fond regard is efficient yet non wholly understood. We investigate here the orientated attachment procedure of ZnO nanocrystals preformed in the gas stage. During the deposition in high vacuity, approximately 60 % of the atoms, which are uncapped, form larger crystals through oriented fond regard. In the present conditions of deposition no selective way for the orientated fond regard is noticed. To examine the driving force of the orientated fond regard, and more specifically the possible influence of the dipolar interaction between atoms, we have deposited the same nanocrystals in the presence of a changeless electric field. The expected consequence was to heighten the fraction of spheres ensuing from the oriented fond regard due to the increased interaction of the atom dipoles with the electric field. The multiscale analytical and statistical analysis ( TEM coupled to XRD ) shows no important influence of the electric field on the organisation of the atoms. We therefore conclude that the dipolar interaction between nanocrystals is non the outstanding driving force in the procedure. Consequently, we argue, in conformity with recent theoretical and experimental probes, that the surface decrease, perchance driven by Coulombic interaction, may be the major mechanism for the orientated fond regard procedure.

Keywords: oriented fond regard, ZnO nanocrystals, TEM, dipolar interaction

1. Introduction

The ability to synthesise mesostructures from nanoparticles as primary edifice blocks is a cardinal issue of both cardinal and technological involvements. One of the most outstanding mechanisms involved in bottom-up schemes is the orientated fond regard ( OA ) procedure. [ 1 ] It is a generic mechanism chiefly observed in iono-covalent stuffs [ 2 ] such as TiO2, [ 3,4 ] ZnO, [ 5,6 ] ZnS, [ 7 ] PbS, [ 8 ] PbSe, [ 9,10 ] i??-Fe2O3 [ 11 ] and YAG [ 12 ] but besides in some metals [ 13 ] and even in natural [ 14 ] and biomineral systems. [ 15 ] Recent plants have demonstrated the ability to synthesise big constructions in a instead controlled manner [ 16 ] such as mesoporous ellipsoids [ 17 ] and legion nanorods or nanowires. [ 5,6,18 ]

However, the chief drive force underlying the OA mechanism is still under argument. Two chief hypotheses have been evoked. The first 1 is the interaction of dipoles carried by the nanoparticles. This is consistent with the fact that OA is chiefly observed in iono-covalent stuffs even though it has besides been reported for metallic atoms. [ 13,19 ] The 2nd chief hypothesis is merely the decrease of the big surface energy of nanoparticles. Whereas direct measurings of atom dipoles of different beginnings have been made [ 20,22 ] and even harvested to self-organize nanoparticles, [ 21 ] no direct grounds of the function of the atom dipole in the OA procedure has been demonstrated. On the reverse, recent measurings [ 9 ] and first rule computations on PbSe nanoparticles [ 10 ] go to demo that the outstanding function in the OA is played by the surface decrease.

In this work we investigate the mechanisms at interest in the OA. In order to examine the influence of the dipolar interaction between atoms, we deposited iono-covalent nanocrystals in the presence or absence of an electric field ( parallel or perpendicular to the substrate ) and compare the formation of big crystalline spheres ensuing from the OA in both instances. Our scheme relies on a multiscale analysis by uniting X-Ray Diffraction ( XRD ) to acquire crystalline information at the macroscopic graduated table and transmittal negatron microscopy ( TEM ) for local composing, crystallographic stage and orientation dealingss. If the dipolar interaction between atoms is the outstanding mechanism in the OA, the application of the external field during the deposition should heighten the common orientation of the atoms and accordingly their fond regard. In order to maximise the conjectural interaction of the external field with the atoms, we have focused on ZnO nanoparticles. Beside its obvious major technological involvement for opto-electronics, [ 23 ] photo-catalysis, [ 24 ] photovoltaics, [ 25 ] ZnO has the advantage of holding a lasting electric dipole minute 11.4 times and 5.21 times larger than those of CdSe and CdS severally [ 20,21 ] and should therefore be extremely sensitive to the influence of an electric field.

2. Methods

ZnO nanocrystals have been preformed in the gas stage by the LECBD technique ( low energy bunch beam deposition ) and later deposited in a controlled environment ( high vacuity ) . This process allows us to work with ligand-free stoichiometric nanocristals. [ 26 ] The synthesis technique used here has been detailed in old work. [ 27 ] Briefly, a ZnO mark made from a sintered pulverization ( 99.99 % pure ) is ablated by a pulse YAG: Nd optical maser ( 10 Hz repeat rate, 10 N pulse continuance ) . The extirpation creates a plasma of Zn and O species which is foremost cooled by the uninterrupted injection of a buffer gas at 20 mbar ( see back uping information ) . The buffer gas is a mixture of 75 % He and 25 % O2 to guarantee the resulting bunchs are stoichiometric26. While chilling the plasma, the buffer gas induces the formation of nucleation embryos ( dimers and trimers ) . The plasma later undergoes a supersonic adiabatic enlargement while traveling from the nucleation chamber at 20 mbar to the high vacuity deposition chamber at 10-7 mbar through a micrometric nose. During the enlargement, the formation of bunchs is achieved by accumulation of embryos and atoms. The preformed bunchs are so deposited on any given substrate without devastation since their kinetic energy per atom is several orders of magnitude lower than the adhering energy per atom inside the bunchs. Indeed, the speed of the bunchs is estimated to be about 500 m/s, matching to a kinetic energy per Zn or O atom of the order of 50 meV, which has to be compared to the covalent adhering energy amounting to a few electron volt. Let us stress that up to now this technique performed to synthesise bunchs of metallic and covalent stuffs has ever led to nanostructured movies in which the person preformed bunchs retain their unity. [ 27 ] This fact is referred to as the “ memory consequence ” .

For deposition in a inactive electric field analogue to the substrate, we have applied during the deposition a 5 kilovolt prejudice between two metallic electrodes ( 1 mm tallness ) separated by 1 millimeters, placed 0.8 millimeters above the substrate ( TEM holey C grids with a thin movie of formless C from Ted Pella inc. ) and separated from it by an insulating spacer. For application of a field perpendicular to the substrate, the same set up has been used but with both electrodes connected to the 5 kilovolt high electromotive force and the sample holder to the land. Figure 1 shows both experimental set up constellations every bit good as the matching electric field maps. One can see a major difference between the two constellations: because of the conductive nature of the TEM grid, no planar electric field can be at the sample surface. Therefore, the two-dimensional field is merely operative in pointing the nanoparticle dipoles above the surface. On the contrary, when the electric field is applied sheer to the substrate, its magnitude is maximum at the sample surface. Its consequence is maximum and all the more efficient as the field is present wholly through the deposition.

The TEM analysis has been performed utilizing a JEOL 2010F microscope equipped with a field emanation gun runing at 200 keV. High declaration images were acquired with a Gatan CCD Orius camera and analyzed utilizing Digital Micrograph package. Energy Dispersive Spectroscopy ( EDS ) spectra were collected with an Oxford Instruments INCA system. Size distribution was determined by geting bright field images of big zones of the sample, at random. The nanoparticle diameters were so measured on the images after cleavage on the gray degree. To specify the size and country of the crystalline domains in high declaration TEM images ( HRTEM ) , we have considered that two atoms in contact with indistinguishable reticular planes showing an orientation mismatch of less than 5A° were oriented and attached. The XRD analysis has been carried out on a Brucker D8 setup in the Bragg-Brentano constellation, utilizing the Cu ki?? radiation.

3. Evidences of orientated fond regard

Figure 2 ( top ) presents a TEM image of single nanoparticles. The corresponding size distribution is a log-normal jurisprudence peaked at 6 nanometers in diameter, typical of our accumulation growing procedure. High declaration TEM images ( right panels of figure 2 ) show that the bunchs are crystallized in the wurtzite construction and in situ XPS analyses published [ 26 ] revealed the resulting movie is stoichiometric. Furthermore, energy diffusing spectrometry ( EDS ) has shown that there is no important composing fluctuation from one single atom to another ( see back uping information ) .

The wurtzite construction is farther confirmed by XRD analysis on the bunch assembled movies. However, as can be seen on Figure 3, the diffractogram contains two distinguishable parts, a low magnitude one characterized by wide extremums and a high magnitude one made of crisp contemplations matching to ( 10-10 ) , ( 0002 ) and ( 10-11 ) diffracting planes. The weak part corresponds to bunchs with a average size of 6 A± 1 nanometer as deduced from the full-width at half-maximum ( FWHM ) utilizing Debye-Scherrer ‘s equation and presuming crystalline spheres without defects. This average size is in full understanding with the manner of the lognormal distribution determined from TEM micrographs. The same process applied to the intense crisp extremums gives a average size of about 20 nanometers for the corresponding diffracting crystalline spheres. Consequently, some bunchs ( 64 A± 4 % harmonizing to the ratio of the country of the crisp contemplation extremums with the entire country of the XRD signal ) among the movie have attached to organize larger crystals and others have non. To corroborate further this observation, we have co-deposited the same sum of bunchs in a MgO matrix ( generated by negatron gun vaporization ) . The deposition rates were chosen so that the single ZnO bunchs are separated by several 10s of nanometres. The corresponding XRD diffractogram ( cf. figure 3 ) is indistinguishable to the low magnitude part of the old sample. Besides, the TEM analysis of this sample gives a log-normal jurisprudence for the size scattering ( cf. figure 2 underside left ) with a average diameter of 4.5 nanometers, in just conformity with the value obtained for the stray bunchs sing that the contrast between the ZnO atoms and the MgO matrix is instead hapless. We therefore conclude that some bunchs among the ensemble interact to organize larger atoms and that this interaction occurs during the deposition ( movie formation ) and non in the gas stage.

To acquire more penetration into the formation of the larger atoms we have analyzed by HRTEM thicker sedimentations in which the incident nanoparticles are no longer isolated. Figure 4 nowadayss some selected micrographs. On these images the orientated fond regard is clearly observed. In peculiar, in Figure 4 B ) two distinguishable atoms have attached sheer to the [ 0001 ] axis and the resulting construction presents a constriction at the fond regard location. A little mismatch of their several lattices can be distinguished every bit good. In some instances the orientated fond regard is non as perfect and leads to the formation of twin boundaries ( californium. fig. 4f ) . This phenomenon has already been reported as a coevals mechanism of crystalline defects ( stacking mistakes, disruptions ) 3. The presence of big crystalline spheres, dwelling of several initial bunchs, is clearly seeable as the deposited sum of affair additions ( see fig. 4a ) . Several illustrations are besides given in fig. 5 and in the back uping information.

Contrary to few old surveies [ 5 ] and to recent numerical simulations [ 31 ] , the OA in our instance does non happen along specific waies. This absence of texture is clearly evidenced on the XRD diffractograms ( cf. figure 3 ) where the crisp contemplation extremums, matching to the big diffracting spheres, present strength ratios near to those of a pulverization. This is farther evidenced by HRTEM in figure 5 and in the back uping information, where no specific orientation of the fond regard axes is observed. For case, in fig. 5b and degree Celsiuss, we can separate two spheres with their ( 10-10 ) planes in the Bragg diffraction orientation. However, the sphere of fig. 5b is extended along these planes, proposing an orientated fond regard of other planes, whereas the sphere of fig. 5c is extended along the ( 10-10 ) way and therefore seems to ensue from an OA of the ( 10-10 ) planes.

4. Possible beginning of the orientated fond regard: influence of the dipolar interaction

At this point, it is established that ZnO bunchs, preformed in the gas stage, tend to garner through the OA mechanism during the deposition without any discriminatory fond regard planes. Since the atoms are passivated neither by cresting ligands nor by air wet ( because of the deposition in high vacuity ) we can govern out any chemical affinity between some cresting shells or the encompassing medium. As elicited antecedently we are left chiefly with two major hypotheses to explicate the driving force of the OA mechanism. The first 1 is an interaction of dipolar beginning and the 2nd one is of chemical beginning, viz. the obliteration of unstable aspects.

The nanoparticle dipole can hold three distinguishable causes. First, it can arise from the crystal lattice. This is the instance of wurtzite constructions with a non-ideal lattice parametric quantity u/a ratio. The effect is the being of a cell dipole that scales as the volume of the nanoparticle, as reported for CdSe. [ 20,21 ] The 2nd possible cause is the presence of polar aspects. Polar aspects can be obtained either of course from the ionic crystal, such as { 111 } planes in the rocksalt construction or { 0001 } planes in the wurtzite construction or from non-polar aspects losing one or few ions. The last possible beginning of a dipole is the anisotropic form of a impersonal nanoparticle. [ 22 ] In all those instances, the dipole graduated tables as the diameter of the atom. However, merely dipoles arising from the cell or the { 0001 } aspects, and accordingly oriented along the degree Celsius axis, can take to oriented fond regard since they are linked to the crystal web. The other dipoles are stochastically oriented with regard to the crystal web and are therefore non expected to bring on specific common orientation between atoms. Hence they can non take to orientated fond regard.

To look into the possible influence of dipolar interactions, we have deposited the same nanoparticles in the presence of a inactive electric field, either analogue or perpendicular to the sample surface and compared their assembly to that of the old nanoparticles deposited without any electric field. The value of the electric field E was set to 5 MV/m and 6.25 MV/m in the analogue and perpendicular geometries severally so as to accomplish an interaction between any dipole carried by the atoms and the electric field larger than the thermic activation energy at room temperature. Indeed for a 6 nm diameter ZnO atom, the cell piezoelectric dipole D, which is relative to the atom volume, sums to 1700 Debye sing a piezoelectric self-generated polarisation [ 29,30 ] of 0.057 C/m2. The corresponding energy of interaction with the electric field is D.E, amounting to 0.16 electron volt ( parallel geometry ) or 0.2 electron volt ( perpendicular geometry ) , a value much larger kBT at 300K ( 26 meV ) . On the other manus, the surface dipole S ensuing from simple charges located at opposite sites along the atom diameter would amount for the same atom to 283 Debye giving an interaction energy of 30 meV ( parallel geometry ) or 37.5 meV ( perpendicular geometry ) , a value somewhat larger than kBT at room temperature. Therefore, if some dipoles of any beginning are present among the atoms, the application of the electrical field should modify their common orientation and accordingly their attachment chance.

However, upon landing of the atoms on the C movie, the releasing of the kinetic energy may unhinge the orientation presumptively induced by the electric field. To look into this hypothesis, we have plotted in figure 6 the fraction of diffracting atoms, either single or attached, for which we can detect a given { hkl } reticulate plane household in diffraction status. For the { 10-11 } , { 10-10 } , { 10-12 } and { 10-13 } plane households, the alterations observed whether the electric field is applied sheer or parallel to the sample surface are statistically important ( see back uping information for the inside informations of the statistical analysis ) . Consequently, we can asseverate that the orientation of the field has an consequence on the atom concluding orientation. Furthermore, the fluctuations are consistent with the expected 1s. Indeed, when the electric field is perpendicular the sample, since, as stated antecedently, the dipole interacting with the field is needfully along the c-axis of the cell, we expect more atoms with their c-axis analogue to the field and therefore we should detect more planes parallel to this axis in diffraction status. This is the instance for the ( 10-10 ) planes. Conversely, all the others planes, stoping the c-axis such as the ( 10-11 ) , ( 10-12 ) and ( 10-13 ) planes, are more often observed when the field is parallel to the sample surface. This statement should besides be true for the ( 0002 ) planes. However, the frequence of observation of these planes is indistinguishable for both orientations of the electric field. This may be due to the uncertainness peculiar to the ( 0002 ) planes in the assignment of the diffraction points in the FFT images. Anyhow, the decision of this statistical analysis is that the electric field amplitude is big plenty so as to modifiy the atom orientation.

The ultimate inquiry is therefore whether the electric field can heighten the OA procedure. To reply this inquiry, a robust statement is to mensurate and compare the proportions of crystalline mono-domains among the atoms observed in samples deposited with and without the electric field. The proportion of the country related to nanoparticles that are oriented and attached is 54 % , 54.7 % and 55 % for the samples deposited without electric field and with the planar and perpendicular Fieldss, severally. No important difference is observed from a statistical point of position. These values are besides in reasonably good understanding with the value of 64 A± 4 % obtained from the XRD analysis mentioned antecedently. We can therefore govern out the possible influence of a dipole carried by the incident bunchs on the OA. This of import statement is in conformity with recent experiments and simulations. [ 31 ] In peculiar, the work of Li and colleagues [ 16 ] emphasizes the consequence of surface decrease in liquids instead than dipolar interaction by in situ TEM analysis. Besides the simulations from Schapotschnikow et Al. [ 10 ] on PbSe nanocrystals and from Zhang and Banfield on several nanocrystals [ 31 ] go to demo that the outstanding mechanism is surface decrease and non dipolar interaction.

If we sum up the old observations, we have established that OA occurs during the deposition of uncapped ZnO nanoparticles preformed in the gas stage in high vacuity, on the substrate ( non the gas stage ) . The OA procedure does non happen selectively along the [ 0001 ] way as predicted for standard conditions [ 31 ] at thermodynamic equilibrium. Besides, since the application of an external electric does non better the OA efficiency, we would instead believe that the ascertained OA consequences from the obliteration of unstable surfaces of next atoms. To explicate these statements, we can see a bed of ZnO nanocrystals deposited on a substrate ( as depicted in figure 7 ) onto which other nanoparticles are later encroaching during the deposition. The deposition is evidently a procedure where the contact nanoparticles are non free to travel, rotate and chose the best orientation to attach ( no thermodynamic equilibrium ) . However, when a subsequent bunch hits the already present nanoparticles, it transfers some kinetic energy which allows the deposited bunchs to travel and revolve for a really short period. During this clip, the high Coulombic interaction between bunchs ( all the higher as they are at close scope ) can take to rearrangement and to the oriented fond regard of the two bunchs if they are non ab initio excessively confused. In other words, we suspect the subsequent contact bunchs and buffer gas molecules to supply some excess energy and therefore some grades of freedom to the already present bunchs ; a freedom of gesture which has been pointed out by Li and colleagues [ 16 ] in their survey in liquids as a cardinal parametric quantity in the OA procedure.

5. Decisions

In drumhead, we have studied the organisation of ZnO nanocrystals preformed in the gas stage. We have observed that during the deposition in high vacuity about 60 % of the atoms, which have uncapped surfaces, signifier larger crystals due to the OA procedure. In our conditions of deposition, no selective way for the OA is noticed. To examine the driving force of the OA, and more exactly the possible influence of the dipolar interaction between atoms, we have deposited the same nanocrystals in the presence of a changeless electric field. The expected consequence was to heighten the fraction of spheres ensuing from the OA due to the increased interaction between the atom dipoles and the electric field. Despite the cogent evidence that he electric field orientation controls the atom orientation, no important consequence has been observed. We therefore conclude and confirm in conformity with recent theoretical and experimental probes on other iono-covalent systems that the dipolar interaction between nanocrystals is likely non a outstanding driving force in the OA procedure. Rather, the surface decrease, perchance driven by Coulomb interaction, is the chief mechanism for the OA. This statement is a major fact in order to command the growing of super-architectures and mesostructures from initial nanocrystals

Support Beginnings

This work was supported by the INSA Lyon BQR undertaking 2012. KMV acknowledges the Institut Universitaire de France ( IUF ) for fiscal support.


The writers acknowledge the PLYRA ( plateforme lyonnaise de recherche Sur lupus erythematosuss agregats, hypertext transfer protocol: //www-lpmcn.univ-lyon1.fr/plyra/ ) installation for entree to the nanoparticle generators. Thankss are due to the CLYM ( Centre Lyonnais de Microscopie hypertext transfer protocol: //www.clym.fr ) for the entree to the microscope JEOL 2010F. The writers besides acknowledge the aid of Qian Rong in the analysis of TEM cliches.

Supporting Information

LECBD set up ; EDS local analysis of the ZnO nanocrystals ; HRTEM images of big as-deposited nanoparticles ; presence of big crystalline spheres ensuing from OA and their common orientation and extension ; statistical analysis of the consequence of the orientation of the electric field on the atom orientation. This stuff is available free of charge via the Internet at hypertext transfer protocol: //pubs.acs.org.

Matching Writer

* To whom correspondence should be addressed: tel. +33 4 72437472. Electronic mail: bruno.masenelli @ insa-lyon.fr

aˆ Present addressA : Institut Neel, CNRS/UJF UPR2940, 25 herb of grace diethylstilbestrols martyrs BP166, 38042 Grenoble Cedex 9

Figure captionsA :

Figure 1: strategy of the experimental set up used to use the inactive electric field during the deposition of the bunchs. The field is changeless, amounting to 5 MV/m ( a 5kV prejudice across a 1 millimeter spread ) . D stands for the dipole carried by the nanoparticles. Two constellations with the electric field analogue or perpendicular to the sample have been used. The corresponding maps of field strength are presented on the right portion.

Figure 2: Top left: bright field TEM image of the as-deposited ZnO bunchs and the corresponding size distribution map ( inset ) . Bottom left: bright TEM image and size distribution map ( inset ) of the ZnO bunchs dispersed in MgO matrix. Top and bottom right: two illustrations of HRTEM images of single bunchs. The atoms are absolutely crystallized in the wurtzite construction, as evidenced by the FFT of the images. The atoms of the top and bottom right panels have their zone axis oriented along the [ 01-10 ] and [ 0001 ] waies severally.

Figure 3: XRD spectra of the ZnO bunchs assembled movie ( top ) and of the same bunchs dispersed in a MgO matrix ( underside ) . The spectrum of the bunch assembled movie nowadayss two distinguishable parts, one identical to that of the bunchs dispersed in MgO with wide extremums characteristic of little crystalline spheres and a 2nd 1 with crisp extremums declarative mood of big crystalline spheres. The crisp part sums to 64 % of the overall spectrum.

Figure 4: a ) a typical big crystalline sphere ensuing from the OA of several initial little bunchs. The pointers labeled with Numberss 1 to 4 precise the extension of the sphere ; B ) crystalline sphere ensuing from the OA of two distinguishable bunchs. The [ 0001 ] way is indicated by the pointer. A little mismatch of the reticulate planes can be seen ; degree Celsiuss ) two affiliated atoms. The pointer highlights the attachment plane ; vitamin D ) other illustration of several atoms attached to organize a larger faceted comain. On the top left portion of the image, a little atom attached to the big bunch can be distinguished ; vitamin E ) three affiliated atoms. The aspects of the atoms are indicated by flecked lines ; f ) Two illustrations of twin boundaries ensuing from the orientated fond regard of ZnO nanocrystals. The yellow dotted lines indicate the locations of the duplicate boundaries ; H ) several atoms organizing a big crystalline sphere. The fact that the sphere consequences from the fond regard of several atoms is evidenced by the contour of the sphere. Note that the atom labeled 3 is non in perfect lucifer with atom 2.

Figure 5: a ) HRTEM image of several crystalline spheres ensuing from the OA ( top left ) . The distinguishable spheres are seeable on the images reconstructed from the filtered FFT image ( B ) to e ) ) . The pointer highlights the way of the sphere extension. The crystalline sphere in B ) is extended along the ( 10-10 ) diffracting planes. On the contrary, the sphere in degree Celsius ) is extended sheer to these planes, proposing that the OA is non selectively oriented in our experiments ; vitamin D ) and vitamin E ) are spheres with their ( 1100 ) and ( 10-11 ) planes in the Bragg diffraction status. In vitamin D ) the sphere extension is perpendicular to the ( 1100 ) planes while it is perpendicular to the [ 10-11 ] way in vitamin E ) .

Figure 6: consequence of the electric field orientation on the atom orientation: fraction of diffracting atoms, either single or attached, for which we can detect a given { hkl } reticulate plane household in diffraction status. Full bars: field perpendicular to the sample, striped bars: field analogue to the sample.

Figure 7: proposed strategy of the OA procedure happening during the deposition of bunchs preformed in the gas stage: a ) particles 1 and 2 are already deposited, touching but non oriented. Particle 3 is geting from the bunch beam. B ) Upon encroaching, atom 3 releases some kinetic energy to the other atoms. This energy extra sets them free from the substrate interaction and their common interaction. Particles 1 and 2 are free to travel and research several constellations of orientation for a short period of clip. If, during this period, they find an orientation of fond regard, taking to the decrease of surface, OA will be promoted. degree Celsius ) Particles 1 and 2 are now oriented and attached while atom 3 has landed on the substrate.

[ 1 ] Y. Yin, A.P. Alivisatos, Nature 2005, 437, 664

[ 2 ] Z. Li, F. Xu, X. Sun, W. Zhang, Crystal Growth & A ; Design 2008, 8, 805

[ 3 ] R.L. Penn, J.F. Banfield, Science 1998, 281, 969

[ 4 ] R.L. Penn, J.F. Banfield, Geoch. Cosm. Act. 1999, 63, 1549

[ 5 ] C. Pacholski, A. Kornowski, H. Weller, Angew. Chem. Int. Ed. 2002, 41, 1188

[ 6 ] X. Liu, Z.A Jin, Z. Liu, K. Yu, S.A Bu, Appl. Surf. Sci. 2006, 252, 8668

[ 7 ] F. Huang, B. Gilbert, H. Zhang, J.F. Banfield, Phys. Rev. Lett. 2004, 92, 155501

[ 8 ] C. Schliehe, B.H. Juarez, M. Pelletier, S. Jander, D. Greshnykh, M. Nagel, A. Meyer, S. Foerster, A. Kornowski, C. Klinke, H. Weller, Science 2010, 329,550

[ 9 ] M.A. Van Huis, L.T. Kunneman, K. Overgaag, Q. Xu, G. Pandraud, H.W. Zandbergen, D. Vanmaekelberg, Nanolett. 2008, 8, 3959

[ 10 ] P. Schapotschnikow, M.A. new wave Huis, H.W. Zandbergen, D. Vanmaekelbergh, T.J.H. Vlugt, Nanolett. 2010, 10, 3966

[ 11 ] C. Frandsen, C.R.H. Bahl, B. Lebech, K. Lefmann, L.T. Kuhn, L. Keller, N.H. Andersen, M. von Zimmermann, E. Johnson, S.N. Klausen, S. Morup, S. Phys. Rev. B 2005, 72, 214406

[ 12 ] N. Jia, X. Zhang, W. He, W. Hu, X. Meng, Y. Du, J. ; Jiang, Y. Du, J. All. Comp. 2011, 509, 1848

[ 13 ] A. Halder, N. Ravishankar, Adv. Mat. 2007,19,1854

[ 14 ] J.F. Banfield, S.A. Welcj, H. Zang, T.T. Ebert, R.L. Penn, Science 2000, 289, 751

[ 15 ] C.E. Killian, R.A. Metzler, Y.U.T. Gong, I.C. Olson, J. Aizenberg, Y. Politi, F.H. Wilt, A. Scholl, A. Young, A. Doran, M. Kunz, N. Tamura, S.N. Coppersmith, P.U.P.A. Gilbert, J. Am. Chem. Soc. 2009, 131, 18404

[ 16 ] D. Li, M.H. Nielsen, J.R.I. Lee, C. Frandsen, J.F. Banfield, J.j. De Yoreo, Science 2012, 336, 1014

[ 17 ] Y. Liu, D. Wang, Q. Peng, D. Chu, X. Liu, Y. Li, Inorg. Chem. 2011, 50 5841

[ 18 ] M. Yang, G. Pang, J. Li, L. Jiang, S. Feng, Eur. J. Inorg. Chem. 2006, 3818

[ 19 ] S.K. Yang, W.P. Cai, G.Q. Liu, H.B. Zeng, J. Phys. Chem. C 2009, 113, 7692

[ 20 ] L-S. Li, A.P. Alivisatos, Phys. Rev. Lett. 2003, 90, 097402

[ 21 ] K.M. Ryan, A. Mastroianni, K.A. Stancil, H. Liu, A.P. Alivisatos, Nanolett. 2006,6, 1479

[ 22 ] M. Shim, P. Guyot-Sionnest, J. Chem. Phys. 1999, 111, 6955

[ 23 ] A. Tsukazaki, A. Ohtomo, T. Onuma, M. Ohtani, T. Makino, M. Sumiya, K. Ohtani, S.F. Chichibu, S. Fuke, Y. Segawa, S. Ohno, H. Koinuma, M. Kawasaki, Nat. Mat. 2005, 4, 42

[ 24 ] C.Hariharan, Appl. Catal. A 2006, 304, 55

[ 25 ] S.D. Oosterhout, M.M. Wienk, S.S. new wave Bavel, R. Thiedmann, L.J.A. Koster, J. Gilot, J. Loos, V. Schmidt, R.A.J. Janssen, Nat. Mat. 2009, 8, 818

[ 26 ] D. Tainoff, B. Masenelli, O. Boisron, G. Guiraud, P. Melinon, J. Phys. Chem. C 2008, 112, 12623

[ 27 ] A. Perez, P. Melinon, V. Dupuis, L. Bardotti, B. Masenelli, F. Tournus, B. Prevel, J. Tuaillon-Combes, E. Bernstein, A. Tamoin, N. Blanc, D. Tainoff, O. Boisron, G. Guiraud, M. Broyer, M. Pellarin, N. Del fatti, F. Vallee, J-L Vialle, C. Bonnet, P. Maioli, A. Crut, C. Clavier, J. L. Rousset, F. Morfin, Int. J. Nanotechnol. 2010, 7, 523

[ 28 ] F. Huang, H. Zhang, J.F. Banfield, Nanolett. 2003, 3, 373

[ 29 ] F. Bernardini, V. Fiorentini, D. Vanderbilt, Phys. Rev. B 1997, 56, R10024

[ 30 ] Y. Noel, C.M. Zicovich-Wilson, B. Civalleri, Ph. D’Arco, R. Dovesi, Phys. Rev. B 2001, 65, 014111

[ 31 ] H. Zhang, J. F. Banfield, J. Phys. Chem. Lett. 2012, 3, 2882

Leave a Reply

Your email address will not be published. Required fields are marked *