TiO2/Fe2O3异质结薄膜的制备及其光电特性的研究

通过水热法成功在FTO上制得Ti O2/Fe2O3异质结薄膜,采用场发射扫描电子显微镜(FESEM)、X射线衍射仪(XRD)、紫外-可见吸收光谱(UV-Vis)分析测试手段对样品的形貌和结构进行了表征。结果表明,Ti O2/Fe2O3异质结是由直径约200~300 nm的Ti O2纳米棒镶嵌着Fe2O3纳米颗粒组成。通过光电流测试,证明Ti O2/Fe2O3异质结的可见光光电转换效率相比Ti O2明显提高,并对Ti O2/Fe2O3异质结的光电转换机理进行了分析。     

交变磁场诱导自组装超结构Ni0.5Zn0.5Fe2O4/PAA复合纳米线

采用沸腾回流法制备了单相Ni0.5Zn0.5Fe2O4颗粒,并对其进行了PAA包覆,得到了Ni0.5Zn0.5Fe2O4/PAA复合纳米颗粒,并在交变磁场的诱导下进行自组装,得到了一维纳米线。室温磁滞回线表明,PAA的包覆降低了Ni0.5Zn0.5Fe2O4颗粒的饱和磁化强度和矫顽力,分别为21.1 emu/g和3.2 Oe。偏光显微照片表明,在交变磁场磁性模板自我强化作用的影响下,制备的软磁铁氧体复合物在0.05 T的磁场中仍有较敏感的响应,形成一维纳米线。SEM照片表明,纳米线直径200 nm,长径比大于100,线体本身则由纳米复合物形成的小团聚体首尾相连构成。     

微乳液法制备几种纳米软磁铁氧体粉体及磁性能研究

采用水/Triton X-100/ 环己烷/正己醇微乳体系制备了尖晶石型NiFe2O4、Ni0.5Zn0.5Fe2O4、MnFe2O4、Mn0.5Zn0.5Fe2O4纳米粉体,利用X射线衍射(XRD)、透射电子显微镜(TEM)、Zeta电位仪、振动样品磁强计(VSM)等对纳米粉体的结构和磁性能进行表征.研究结果表明:微乳液法制备的纳米软磁铁氧体晶粒结构完整、粒径细小且分布均匀(粒径范围在30～80 nm),合适的煅烧温度为500 ℃;在室温下埘制备的几种软磁铁氧体进行磁性能测定发现,与其他制备方法相比,采用微乳液法制备的纳米软磁铁氧体的比饱和磁化强度较高,比剩余磁化强度、矫顽力较低,软磁性性能较佳.     

磁性Fe3O4@TiO2/ZnO的制备及光催化性能研究

通过水热法制备磁性Fe3O4@C纳米微球,分别将TiO2和ZnO负载到微球上得到磁性Fe3O4@TiO2/ZnO催化剂.利用扫描电镜、红外光谱和紫外漫反射光谱表征催化剂的形貌和结构性能.紫外漫反射光谱显示磁性Fe3O4@TiO2/ZnO的吸收带边红移,表明催化剂可以在更高的波长范围内吸收光波,且禁带宽度变大表明光生电子和空穴具有更强的氧化还原能力,因此具有更强的光催化活性.相比于磁性Fe3O4@TiO2,磁性Fe3O4@TiO2/ZnO催化剂对罗丹明B的降解率从65.33;增加到98.11;.循环使用5次后,磁性Fe3O4@TiO2/ZnO催化剂对罗丹明B的降解率仍保持92.05;,说明该催化剂具有易于回收和良好的循环稳定性.     

WO3颗粒修饰TiO2纳米锥的制备及其光催化性能研究

采用水热法、浸渍法后退火的方法制备WO3-Ti O2纳米锥薄膜。紫外-可见光谱结果表明生成的WO3-Ti O2纳米锥薄膜的吸收边延长到可见光范围,达到480 nm。光催化结果表明,样品WO3-Ti O2纳米锥薄膜比纯Ti O2纳米锥薄膜具有更好的光催化性能,经过10次循环降解实验后,其降解率仍然能够达到96.8%,显示其具有良好的循环稳定性。     

Ni离子注入SiO_2的表面形貌和光学吸收性能研究

室温下,将能量为60 keV,剂量范围在1×1016~1×1017/cm2的Ni离子注入到SiO2中。随后将样品在Ar气中退火(400~1000℃)。采用原子力显微镜(AFM),掠入射X射线衍射(GXRD),紫外-可见分光光度计(UV-Vis)对退火前后样品的表面形貌,Ni纳米颗粒的形成和热演变过程以及样品光吸收性能进行分析表征。结果表明:剂量为1×1016/cm2的样品退火前后均未能形成纳米颗粒;剂量为5×1016/cm2和1×1017/cm2的样品中形成了纳米颗粒,退火后颗粒长大,样品表面凸起(Ni纳米颗粒)高度增加,数量减少。SiO2中Ni纳米颗粒的光吸收带在310~520 nm,800℃后光吸收带变得明显且伴随峰位蓝移。经1000℃退火后,Ni纳米颗粒被热分解的O氧化为NiO纳米颗粒,NiO纳米颗粒的光吸收带位于300 nm附近。     

钒酸铜纳米线的制备及光吸收性能

以CuCl2和NH4VO3为原料,采用水热法制备了α-CuV2O6纳米线.采用X射线衍射(XRD)研究了所得α-CuV2O6纳米线的晶相特征,采用场发射扫描电镜(FE-SEM)及透射电镜(TEM)观察产物的微观形貌,利用X-射线能谱(EDS)及X-射线光电子能谱(XPS)对样品的组成进行了分析,并采用紫外-可见漫反射(UV-vis DRS)测定了样品的光吸收性能.紫外-可见漫反射测试显示α-CuV2O6纳米线具有较宽的紫外-可见光吸收范围.     

钒酸铁纳米棒的制备及光吸收性能研究

以Fe(NO3)3·9H2O和NH4VO3为原料,采用水热法制备了FeVO4纳米棒。采用X射线衍射(XRD),热重分析(TG),X射线光电子能谱(XPS)及场发射扫描电子显微镜(FE-SEM)对样品的物相组成和微观形貌进行了表征。并采用紫外-可见漫反射测试(UV-vis DRS)测定了样品的光吸收性能,DRS结果显示FeVO4纳米棒具有较宽的紫外-可见光吸收范围,结合Tauc方程计算得出FeVO4纳米棒的光学带隙为2.13 eV。光催化降价甲基橙性能测试显示经90 min紫外灯照射,对甲基橙的降解率为93.6%。     

离子液体[Bmim]BF4辅助制备超顺磁性Fe3O4纳米粒子

以七水硫酸亚铁(FeSO4·7H2O)与六水三氯化铁(FeCl3·6H2O)为原料,离子液体1-丁基-3-甲基咪唑四氟硼酸盐([Bmim] BF4)为添加剂,70℃下反应2h制备了Fe3O4纳米粒子.通过X射线衍射仪(XRD)、傅里叶红外光谱(FT-IR)、扫描电子显微镜(SEM)、透射电子显微镜(TEM)以及热重分析(TG)等方法对样品的结构和形貌进行表征,并测试了所合成样品的磁性能.实验结果表明:离子液体辅助制备的Fe3O4纳米粒子形貌较为均一,呈近似球状,平均直径约为14 nm,产品在室温下表现出超顺磁性,饱和磁化强度为60.66 emu/g.利用密度泛函理论(DFT)计算模拟了Fe3O4分别与离子液体和水相互作用的电子结构,发现离子液体通过阴离子的桥联,更易吸附在Fe3O4晶粒表面.     

盐酸对共沉淀法合成单分散性纳米四氧化三铁的改性研究

采用共沉淀法合成了粒径为6～10 nm的Fe3O4粒子.借助X射线衍射、红外光谱分析和透射电子显微镜等对其进行了表征.盐酸对纳米Fe3O4分散性的影响通过透射电镜和紫外可见吸收光谱进行表征.结果表明:盐酸对纳米Fe3O4的分散性有很大影响.这种作用机理通过Zeta电位进行验证,表明颗粒的分散性和稳定性随扩散双分子层的厚度而变化,而且,改性后的纳米Fe3O4显示了更好地超顺磁性.     

Crystal and Molecular Structures of C6H5CH2SOCH2CONHCH2C6H5 and C6H5SOCH2CON(iC3H7)2

Abstract  The crystal structures for two of the ligands C₆H₅CH₂SOCH₂CONHCH₂C₆H₅ (1) and C₆H₅SOCH₂CON(ⁱC₃H₇)₂ (2) have been determined by X-ray diffraction. These compounds crystallize in orthorhombic system with space groups and cell parameters, Pca21(no. 29), a = 8.4600(5) ?, b = 5.3534(5) ?, c = 32.136(2) ?, V = 1455.42(15) ?³ and Pna21(no. 33) a = 17.5563(11) ?, b = 5.7902(4) ?, c = 14.2866(9) ?, V = 1452.30(16) ?³, respectively. These molecules are stabilized in solid state by various intra and intermolecular hydrogen bonding interactions to give polymeric structures. The reported IR spectra of these compounds in solid state could be explained on the basis of the observed intermolecular hydrogen bonding interactions. Index Abstract  The title compounds C₆H₅CH₂SOCH₂CONHCH₂C₆H₅ (1) and C₆H₅SOCH₂CON(ⁱC₃H₇)₂ (2) were prepared by the oxidation of corresponding sulfides with H₂O₂/SeO₂ in methanol and their structures were determined. The structures show that the SO and CO groups are having “anti” configuration in 1 and “syn” configuration in 2. Electronic supplementary material  The online version of this article (doi:) contains supplementary material, which is available to authorized users.     

Enantiomorphism of the Ca3Ga2Ge4O14 compound and comparison of the Ca3Ga2Ge4O14 and Sr3Ga2Ge4O14 structures

The absolute crystal structures of two enantiomorphic forms of the Ca₃Ga₂Ge₄O₁₄ crystals (a = 8.075(1) ?, c = 4.9723(6) ?, space group P321) with the positive and negative senses of the optical activity are determined using X-ray diffraction analysis. The final R factors are as follows: R = 1.75% and R _w = 2.57% for the crystal with the positive sense of the optical activity and R = 1.86% and R _w = 2.78% for the crystal with the negative sense of the optical activity. The replacement of the Ca²⁺ ions by larger Sr²⁺ ions (with the formation of the Sr₃Ga₂Ge₄O₁₄ compound) leads to an anisotropic expansion of the crystal lattice (with a more considerable increase in the lattice parameter a as compared to the lattice parameter c), a change in the occupation of the 1a and 3f positions by the Ga³⁺ and Ge⁴⁺ ions, and symmetrization of the octahedra and tetrahedra forming the structural framework. The shape of the dodecahedron changes so that its size along the polar electric axis 2 increases significantly. This change is the main factor responsible for the increase in the piezoelectric activity of the Sr₃Ga₂Ge₄O₁₄ compound as compared to the piezoelectric activity of the Ca₃Ga₂Ge₄O₁₄ compound. Original Russian Text ? B.V. Mill, A.A. Klimenkova, B.A. Maximov, V.N. Molchanov, D.Yu. Pushcharovsky, 2007, published in Kristallografiya, 2007, Vol. 52, No. 5, pp. 816–823.     

Potentiodynamic polarization studies on amorphous Zr46.75Ti8.25Cu7.5Ni10Be27.5, Zr65Cu17.5Ni10Al7.5, Zr67Ni33 and Ti60Ni40 in aqueous HNO3 solutions

Potentiodynamic polarization studies were carried out on virgin specimens of Zr-based bulk amorphous alloys Zr_46.75Ti_8.25Cu_7.5Ni₁₀Be_27.5 and Zr₆₅Cu_17.5Ni₁₀Al_7.5, and conventional-type binary amorphous alloys Zr₆₇Ni₃₃ and Ti₆₀Ni₄₀ in solutions of 0.2 M, 0.5 M and 1.0 M HNO₃ at room temperature. The values of the corrosion current density (I_corr) for the bulk amorphous alloy Zr_46.75Ti_8.25Cu_7.5Ni₁₀Be_27.5 were found to be comparable with those of Zr₆₅Cu_17.5Ni₁₀Al_7.5 in 0.2 M and 0.5 M HNO₃, but the value of I_corr for the former was almost three times more than that of the latter in 1.0 M HNO₃. In the case of conventional binary amorphous alloys, Ti₆₀Ni₄₀ showed lower value of I_corr as compared to Zr₆₇Ni₃₃ in 0.5 M and 1.0 M HNO₃ and a comparable value of I_corr in 0.2 M HNO₃. In general, the binary Ti₆₀Ni₄₀ displayed the best corrosion resistance among all the alloys in all the cases and the corrosion current density (I_corr) for all the alloys was found to increase with the increasing concentration of nitric acid. It is noticed that the bulk amorphous alloys do not possess superior corrosion resistance as compared to conventional binary amorphous alloys in aqueous HNO₃ solutions. The observed differences in their corrosion behavior are attributed to different alloy constituents and composition of the alloys investigated.     

Ionic conduction in As2S3---Ag2S, GeS2---GeS---Ag2S and P2S5---Ag2S glasses

The glass-forming region in the system P---S---Ag was determined and density, thermal expansion, dc conductivity and the transport number of Ag ions were measured for P₂S₅---Ag₂S glasses found in the P---S---Ag system. The results for the transport number measurement show that P₂S₅---Ag₂S glasses are purely ionic conductors owing to the Ag ion migration, like most of the As₂S₃---Ag₂S and GeS₂---GeS---Ag₂S glasses reported previously. Glass structure and ionic conduction processes in As₂S₃---Ag₂S, GeS₂---GeS---Ag₂S and P₂S₅---Ag₂S glasses are discussed, based on their ionic conductivity and density data. The structural concept of -Ag₂S was applied to these glasses, which suggests that the Ag ions in the glasses are distributed in the available Ag ion sites in the non-conducting framework composed of both S anions and As, Ge or P cations. In each system the ionic conductivity increases linearly with increasing Ag⁺/total cation (%) in glass composition, the determining factor being the activation energy for ionic conduction alone. Thus, the activation energy in these glasses depends predominantly upon the molar ratio of Ag ions to total cation in the glass, irrespective of the kind of system. Small differences in the activation energy among the three systems can be interpreted as arising from differences in the field strength of As, Ge and P cations.     

Phase separation and crystallization in the system SiO2-Al2O3-P2O5-B2O3-Na2O glasses

The phase separation and crystallization behavior in the system (80 − X)SiO₂ · X(Al₂O₃ + P₂O₅) · 5B₂O₃ · 15Na₂O (mol%) glasses was investigated. Glasses with X = 20 and 30 phase separated into two phases, one of which is rich in Al₂O₃-P₂O₅-SiO₂ and forms a continuous phase. Glasses containing a larger amount of Al₂O₃-P₂O₅ (X = 40 and 50) readily crystallize and precipitates tridymite type AlPO₄ crystals. It is estimated that the phase separation occurs forming continuous Al₂O₃-P₂O₅-SiO₂ phase at first, and then tridymite type AlPO₄ crystals precipitate and grow in this phase. Highly transparent glass-ceramics comparable to glass can be successfully obtained by controlling heat treatment precisely. The crystal size and percent crystallinity of these transparent glass-ceramics are 20-30 nm and about 50%, respectively.     

Precipitation of In2O3 nano-crystallites from glasses in the system Na2O/B2O3/Al2O3/In2O3

Glasses in the system Na₂O/B₂O₃/Al₂O₃/In₂O₃ were melted and subsequently tempered in the range from 500 to 700 °C. Depending on the chemical composition, various crystalline phases were observed. From samples without Al₂O₃, In₂O₃ could not be crystallized from homogeneous glasses, because either spontaneous In₂O₃ crystallization occurred during cooling, or other phases such as NaInO₂ were formed during tempering. The addition of alumina, however, controlled the crystallization of In₂O₃. Depending on the crystallization temperature applied, the crystallite sizes were in the range from 13 to 53 nm. The glass matrix can be dissolved by soaking the powdered glass in water. This procedure can be used to prepare nano-crystalline In₂O₃-powders.     

Crystal growth of NdAl3(BO3)4 from K2O/MoO3/Nd2O3/B2O3/KF flux

NdAl₃(BO₃)₄ single crystals were grown by the flux method and the TSSG technique using a K₂O/3MoO₃/B₂O₃/0.5Nd₂O₃/KF flux system. Light-violet clear crystals could be obtained. The effects of fluoride on the growth of NAB crystals were investigated. As the content of KF was gradually increased, the growth form of NAB was changed from the equant to the columnar and the primary crystalline region of NAB was shrinked. At the ratio of KF/K₂O = 0.75, NAB crystals could not be grown.     

Spectroscopic properties of Er-doped Na2O-Sb2O3-B2O3-SiO2 glasses

Spectroscopic properties of Er³⁺-doped Na₂O-Sb₂O₃-B₂O₃-SiO₂ glasses have been investigated for developing 1.5-μm broadband fiber amplifiers. An intense 1.5-μm near infrared emission with a broad full width at half maximum (FWHM) of 88 nm has been obtained for Er³⁺-doped 5Na₂O-20Sb₂O₃-35B₂O₃-40SiO₂ glass upon excitation with a 980 nm laser diode. The obtained emission cross-section of the ⁴I_13/2 → ⁴I_15/2 transition and the lifetime of the ⁴I_13/2 level of Er³⁺ ions are 6.8 × 10⁻²¹ cm² and 0.36 ms, respectively. It is noted that the product of the emission cross-section and the FWHM of the glass, σ_e × FWHM, is as great as 598.4 × 10⁻²¹ cm² nm, which is comparable or higher than that of Er³⁺-doped bismuth-based and tellurite-based glasses. These special optical properties encourage in identifying them as important materials for potential applications in high performance optics and optical communication networks.     

The growth and structure of Pb3Ga2Ge4O14 and Ba3Ga2Ge4O14 single crystals

Conditions for the flux synthesis of Pb₃Ga₂Ge₄O₁₄ and Ba₃Ga₂Ge₄O₁₄ single crystals and their solid solutions Pb_{3 − x} Ba_xGa₂Ge₄O₁₄ are studied. Structural analysis showed that the Ga³⁺-and Ge⁴⁺-cation positions in flux-grown Pb₃Ga₂Ge₄O₁₄ and Ba₃Ga₂Ge₄O₁₄ single crystals are not mixed. __________ Translated from Kristallografiya, Vol. 49, No. 2, 2004, pp. 325–328. Original Russian Text Copyright ? 2004 by Bezmaternykh, Vasil’ev, Gudim, Temerov. This work was presented at the National Conference on Crystal Growth (NCCG-2002, Moscow).     

Thermo-optic properties of B2O3 doped Li2O-Al2O3-SiO2 glass-ceramics

Reduction in the temperature coefficient of the optical path length, dS/dT of Li₂O-Al₂O₃-SiO₂ glass-ceramics with near-zero thermal expansion coefficient was attempted using control of the temperature coefficient of electronic polarizability, ?, and the thermal expansion coefficient, α. The dS/dT value of 2.6 mol% B₂O₃-doped glass-ceramic was 12.5  × 10⁻⁶/°C, which was 0.9 ×  10⁻⁶/°C smaller than that of B₂O₃-free glass-ceramic. On the other hand, reduction in dS/dT through B₂O₃ doping was not confirmed in precursor glasses. Results showed that reduction in dS/dT of the glass-ceramic through B₂O₃ doping is caused by the reduction in ?. The reduction in ? from B₂O₃ doping was probably attributable to numerical reduction in non-bridging oxide ions with larger ? value by the concentration of boron ions in the residual glass phase. In addition, application of hydrostatic pressure during crystallization was effective to inhibit precipitation of β-spodumene solid solution, which thereby decreases dS/dT. The dS/dT value of B₂O₃-doped glass-ceramic crystallized under 196 MPa was 11.7 ×  10⁻⁶/°C. That value was slightly larger than that of silica glass. The α value of this glass-ceramic was smaller than that of silica glass.