稀土元素对提高镍基喷焊合金层耐磨性的效果

通过在喷焊合金粉末中添加稀土合金及其化合物的方法，研究稀土对镍基喷焊合金层性能的影响，探讨了稀土在镍基喷焊合金中应用的可能性，试验结果表明稀土能够明显提高喷焊合金层的耐磨性，细化喷焊合金层组织，改善喷焊合金层和基体的结合状态。     

氧化铈对M80S20喷涂层和喷焊层显微组织及耐磨性的影响

通过光学金相和扫描电镜观察、X射线能谱和X射线衍射分析及干滑动磨擦磨损试验,探讨了稀土氧化物(CeO_2)对M_(80)S_(20)合金喷涂层和喷焊层的显微组织及耐磨性的影响。试验结果表明,加入8％CeO_2可以明显改善喷涂层和喷焊层的显微组织,提高显微硬度和耐磨性。     

La2O3对钛合金表面镍基喷焊涂层组织和性能的影响

采用火焰喷焊技术在钛合金基体上制备了不加La2O3和加4％(质量分数)La2O3两种镍基涂层，分析了它们的显微组织、合金元素的扩散、显微硬度以及耐磨性能。结果表明：La2O3的加人，改善了涂层合金的流动性和显微组织的均匀性，并使涂层与基体的熔合更加明显，结合性能得到进一步提高；虽然一定程度上减弱了基体Ti元素对喷焊层的强化作用，使表层显微硬度略有下降，但磨损失重却较未加La2O3的喷焊涂层下降了20％。     

稀土对喷焊层耐磨性的影响机制

通过在镍基自熔合金粉未中添加微量稀土,研究稀土对喷焊层耐磨性的影响规律及其作用机制。实验结果表明:稀土元素的微合金化作用使喷焊层的组织细化,并使硬质相数量、尺寸、形状及分布发生变化,从而提高喷焊层的耐磨性能。     

纳米Y2O3/钴基合金激光熔覆层的组织

利用5 kW CO2激光器,在Ni基高温合金表面,熔覆纳米稀土氧化物(Y2O3)/钴基合金复合材料,制备了涂层.利用光学显微镜、扫描电镜及透射电镜分析了熔覆层的组织结构.结果表明: 熔覆层的主要相组成为γ-Co,ε-Co,Cr23C6和Y2O3;加入纳米Y2O3,凝固组织由细长的柱状树枝晶转变为较短的树枝晶;纳米Y2O3含量增大至1%时整个断面获得等轴晶组织;纳米Y2O3作为异质形核的核心,细化了组织;纳米Y2O3在熔覆层中分布不均匀,促进了γ-Co向ε-Co的转变;熔覆层的亚结构为堆跺层错.对熔覆层等轴组织形成机制进行了分析.     

La2O3对高碳钢堆焊金属组织与耐磨性的影响

研制了不同La2O3加入量的高碳钢堆焊用药芯焊丝,并制作了相应的堆焊试样。采用金相显微镜对其显微组织进行了观察,X射线衍射仪对其相组成进行了分析,洛氏硬度计和砂带式摩擦磨损试验机对其宏观硬度和耐磨性进行了检测,场发射扫描电子显微镜对其磨损表面进行了观察。结果表明:堆焊金属的组织主要由黑色针状马氏体、白色网状高合金马氏体及残余奥氏体组成。随着La2O3加入量的增加,高合金马氏体含量增加,堆焊金属的硬度和耐磨性也增加,当La2O3加入量为3.44%(质量分数)时,二者均达到最大值。堆焊金属中加入La2O3使初生奥氏体晶粒细化,提高了其基体组织的强硬性,与作为耐磨相的高合金马氏体共同作用,使堆焊金属的耐磨性提高。     

Cu-0.8Cr-xNd(Y)合金耐磨性研究

采用真空熔炼制得Cu-0.8Cr,Cu-0.8Cr-xNd(Y)合金;在考察其组织、强度、硬度的同时,着重研究了Nd,Y对该合金耐磨性能的影响.结果表明:Nd,Y能显著细化晶粒,均化合金区域分布的Cu-Cr共晶组织,提高合金的强度、硬度;Cu-0.8Cr-xNd(Y)合金的耐磨性能随着Nd(Y)的含量从0～0.2%增加而提高,其中Y效果更明显;在耐磨实验工况温度较低时,磨损以擦伤为主,工况温度较高时,磨损以粘焊为主.     

Y2O3纳米粒子/碳纳米管复合体的制备及其催化高氯酸铵热分解

采用化学液相沉淀法制备Y2O3纳米粒子/碳纳米管复合体(Y2O3/CNTC),利用扫描电镜(SEM)和X 射线光电子能谱(XPS)对其结构和成分进行了表征. 结果表明, Y2O3纳米粒子能负载在碳纳米管上,且负载效果较好. 采用差热分析研究了Y2O3/CNTC 对高氯酸铵热分解的催化性能, 结果表明, Y2O3 /CNTC 可显著降低高氯酸铵(AP)的高温分解峰温,表现出对AP 高温分解良好的催化性能. 相同量的Y2O3/CNTC 和纯Y2O3纳米粒子进行对比, Y2O3 /CNTC表现出更强的催化性能.当Y2O3/CNTC的质量分数为4%时,使AP的高温分解峰温提前131.14C[deg].     

同轴静电纺丝技术制备Y_2O_3:Eu~(3+)@SiO_2豆角状纳米电缆与表征

采用同轴静电纺丝技术,以氧化钇、氧化铕、正硅酸乙酯(C8H20O4Si)、无水乙醇、PVP和DMF为原料,成功制备出大量的Y2O3:Eu3+@SiO2豆角状纳米电缆.用TG-DTA,XRD,SEM,TEM和荧光光谱等分析技术对样品进行了系统地表征.结果表明,得到的产物为Y2O3:Eu3+@SiO2豆角状纳米电缆,以无定型SiO2为壳层,晶态Y2O3:Eu3+球为芯,电缆直径约为200nm,内部球平均直径约150nm,壳层厚度约为25nm,电缆长度300μm.纳米电缆内部为球状结构,沿着纤维长度方向有序排列,形貌均一.Y2O3:Eu3+@SiO2豆角状纳米电缆在246nm紫外光激发下,发射出Eu3+离子特征的波长为614nm的明亮红光.对其形成机理进行了初步讨论.     

高频脉冲沉积微晶Ni-20Cr-Y2O3ODS合金涂层

采用高频电脉冲沉积技术在1Cr18Ni9Ti不锈钢表面上沉积了含弥散Y2O3氧化物的纳米级MGH754 ODS合金微晶涂层, 涂层与基体具有冶金结合. 在1 000℃静态空气中100 h恒温氧化实验结果表明:微晶化和添加弥散氧化物促进了涂层中的铬选择氧化形成Cr2O3, 并提高了表面氧化膜的黏附性, 改善了不锈钢抗高温氧化性能.     

Optical properties of nanocrystalline Y2O3:Eu depending on its odd structure

The structure of nanocrystalline Y2O3:Eu prepared by a combustion reaction was analyzed by XRD and high-resolution electron microscopy. Compared with a large-scale particles, 5-nm Y2O3:Eu particles presented as distorted crystallite and rough surfaces. Luminescent and absorption properties of nano-Y2O3:Eu showed remarkably particle size effects. At Y2O3:Eu particle sizes smaller than 10 nm some new results were observed: (a) a red shift of the charge-transfer-state absorption; (b) new emission bands of Eu3+ in the 5D0 --> 7F2 region; (c) luminescent decay of energy level 5D0 of Eu3+ turning to a two-step exponential; and (d) a pronounced increase in quenching concentration and much lower phonon density compared with those of the bulk material. All these phenomena can be attributed to the effect of the softened lattice and surface state of the nanomaterial. The latter was confirmed by stronger excitation by the host absorption after the surface modification.     

Effect of Al2O3 Binder on the Precipitated Iron-Based Catalysts for Fischer-Tropsch Synthesis

A series of iron-based Fischer-Tropsch synthesis (FTS) catalysts incorporated with Al2O3 binder were prepared by the combination of co-precipitation and spray drying technology. The catalyst samples were characterized by using N2 physical adsorption, temperature-programmed reduc-tion/desorption (TPR/TPD) and Mossbauer effect spectroscopy (MES) methods. The characterization results indicated that the BET surface area increases with increasing Al2O3 content and passes through a maximum at the Al2O3/Fe ratio of 10/100 (weight basis). After the point, it decreases with further increase in Al2O3 content. The incorporation of AI2O3 binder was found to weaken the surface basicity and suppress the reduction and carburization of iron-based catalysts probably due to the strong K-Al2O3 and Fe-Al2O3 interactions. Furthermore, the H2 adsorption ability of the catalysts is enhanced with increasing Al2O3 content. The FTS performances of the catalysts were tested in a slurry-phase continuously stirred tank reactor (CSTR) under the reaction conditions of 260℃, 1.5 MPa, 1000 h-1 and molar ratio of H2/CO 0.67 for 200 h. The results showed that the addition of small amounts of Al2O3 affects the activity of iron-based catalysts to a little extent. However, with further increase of Al2O3 content, the FTS activity and water gas shift reaction (WGS) activity are decreased severely. The addition of appropriate Al2O3 do not affect the product selectivity, but the catalysts incorporated with large amounts of Al2O3 have higher selectivity for light hydrocarbons and lower selectivity for heavy hydrocarbons.     

Effects of spray drying on physicochemical properties of milk protein-stabilised emulsions

The effect of spray drying and reconstitution has been studied for oil-in-water emulsions (20.6% maltodextrin, 20% soybean oil, 2.4% protein, 0.13 M NaCl, pH 6.7) with varying ratios of sodium caseinate and whey protein, but with equal size distribution (d₃₂=0.77 μm). When the concentration of sodium caseinate in the emulsion was high enough to entirely cover the oil–water interface, the particle size distribution was hardly affected by spray drying and reconstitution. However, for emulsions of which the total protein consisted of more than 70% whey protein, spray drying resulted in a strong increase of the droplet size distribution. The adsorbed amount of protein ranged from 3 mg m⁻² for casein-stabilised emulsions to 4 mg m⁻² for whey protein-stabilised emulsions with a maximum of 4.2 mg m⁻² for emulsions containing 80% whey protein on total protein, which means that for all these emulsions about one quarter of the available protein was adsorbed at the oil–water interface. The adsorbed amount of protein was hardly affected by spray drying. After emulsion preparation casein proteins adsorbed preferentially at the oil–water interface. As a result of spray drying, the relative amount of β-lactoglobulin in the adsorbed layer increased strongly at the expense of _s1-casein and β-casein. Percentages of _s2-casein and κ-casein in the adsorbed layer remained largely unchanged. The changes in the protein composition of the adsorbed layer as a result of spray drying and reconstitution were the largest when beforehand hardly any whey protein was present in the adsorbed layer and hardly any sodium caseinate in the aqueous phase. Apparently, during spray drying conditions have been such that β-lactoglobulin could unfold, aggregate, and react with other cystein-containing proteins changing the particle size distribution of the emulsions and the composition of the adsorbed layer. It seemed, however, that non-adsorbed sodium caseinate in some way was able to protect the adsorbed casein proteins from being displaced by aggregating whey protein.     

Surface hardness changes induced by O-, Ca- or P-ion implantation into titanium

Titanium or titanium alloys are very attractive biomedical materials. Biocompatible elements of oxygen, calcium and phosphorus were implanted into titanium and changes of surface hardness were measured using an ultra micro indenter (UMIS-2000). A multiple load-partial unload procedure that can reveal a hardness versus depth profile was adopted. Depth profiles of concentration of implanted ions were obtained by SIMS measurement. For O and P implantation, it is observed that the hardness increases with the increases in the dose. O implantation produced the largest increase in hardness, up to 2.2 times higher than the unimplanted titanium. On the other hand, Ca implantation produced only a small increase in the hardness that was independent of the ion dose. The surface oxide layer of a Ca implanted titanium sample was much thicker than the unimplanted samples or those implanted with O and P ions. The depth of maximum hardness increases with increasing energy of implanted ions. The depths of the maximum hardness occur at indentation depths of one-third to one-eighth of the mean ranges of implanted ions.     

喷涂法制备大面积倒置聚合物光伏器件

采用喷涂工艺制备了结构为ITO/ZnO/P3HT∶PCBM/V2O5/Ag(P3HT:聚噻吩;PCBM:6,6-苯基-C61-丁酸甲酯)的大面积倒置光伏器件,有效面积为1.0×1.1 cm2。 光谱测试结果表明,退火处理后,P3HT∶PCBM薄膜吸收显著增强,并且产生一定程度的红移。 采用ZnO和V2O5代替LiF和PEDOT∶PSS(聚(3,4-乙撑二氧噻吩)∶聚苯乙烯磺酸盐)作为器件修饰层,避免了PEDOT∶PSS对ITO的腐蚀和LiF潮解,采用Ag代替Al作为金属背电极避免了Al被氧化。 经过后退火处理器件的效率从1.1%提升至1.65%。 器件的稳定性相对于传统结构有了大幅提升,8周后器件效率只衰减10%。     

Vacuum balance studies of milled material and mechanochemical reactions

The types of change in surface properties and porosity of milled materials having widely different hardness and crystal structure are reviewed. For more intensive milling, the use of vacuum balance techniques in conjunction with X-ray diffraction, optical- and electron-microscopy enables changes in microstructure and phase composition to be determined during mechanochemical reactions.Metallic or non-metallic harder materials (Mohs scale 8–9), such as transition metal nitrides or silicon nitride and boron carbide, increase their surface on milling largely due to brittle fracture, so that the surface area tends towards an upper limiting value with comparatively little development of porosity.Softer materials (Mohs scale 1–2), such as gypsum, china clay(Kaolinite) and hydrated lime and magnesia undergo plastic deformation and strain hardening on longer milling, so that the surface area passes through a maximum before decreasing to an equilibrium value. This is applicable also to materials of intermediate hardness (Mohs scale 3–5), such as calcite, magnesite and dolomite, provided that the milling is sufficiently intensive; the flow and welding processes during the plastic deformation leave the grains non-porous to nitrogen gas, but adsorption of water vapour causes development of porosity, a phenomenon also observed with lunar fines (mainly silicate minerals) which are of somewhat greater hardness but contain amorphous surface layers (cf. Beilby layer) and nuclear particle damage tracks having tubular pores with narrow constrictions forming micropores.More intensive milling can result in crystal transformation and mechanochemical reactions. Thus gypsum is converted to anhydrite, viz., CaSO₄.2H₂O → CaSO₄.2H₂O → γ—CaSO₄ → β—CaSO₄. Calcite, CaCO₃, is converted to aragonite, while calcitic CaCO₃ and magnesite, MgCO₃, form dolomite CaCO₃.MgCO₃.     

Photoresponse of p-type zinc-doped iron(III) oxide thin films

Stable zinc-doped iron(III) oxide thin films that exhibit p-type behavior were synthesized by spray pyrolytic deposition (SPD) on conducting indium-doped tin oxide-coated glass substrate. The highest photocurrent density of 1.1 mA/cm2 was observed at an illumination intensity of 40 mW/cm2 at -0.8 V vs Pt for zinc-doped p-Fe2O3 samples prepared at an optimum substrate temperature of 663 K using an optimum spray time of 70 s. A quantum efficiency of 21.1% at 325 nm was found for SPD samples prepared using a dopant concentration of 0.0088 M zinc nitrate hexahydrate. X-ray diffraction results showed structures of alpha-Fe2O3 and ZnFe2O4. A direct band gap energy of 2.2 eV was found from monochromatic photocurrent density data and agrees closely with the band gap obtained from UV-vis absorption. The X-ray photoelectron spectroscopy results also confirm the presence of zinc dopant (4.0 atomic %) in thin films of zinc-doped p-Fe2O3.     

夹杂物在中高碳钢堆焊金属中成为初生奥氏体非均质形核核心的探讨

采用二维点阵错配度理论,对不同稀土 杂物和中高碳钢堆焊时常见氧化物在熔敷金属中成为初生奥氏体非均质形核核心的有效性进行了分析和计算。成为熔敷金属中初生奥氏体非均质开核核心的夹物以Ｃｅ２Ｏ３．Ｌａ２Ｏ３和Ｃｅ２Ｃ２Ｓ为效,Ａ１２Ｏ３,ＳｉＯ２,ＭｎＯ和ＣｅＳ为无效。     

A Model for Simultaneous Homogeneous and Heterogeneous Nucleation in the Case of Slow Reaction Rate

(Gd(x)Y(1-x))(2)O(3):Eu [x=0, 0.25, 0.5, 0.75, 1.0] phosphor particles with 6 at.% Eu dopant of total concentration were prepared using spray pyrolysis. The effects of composition on the morphology, crystallinity, and photoluminescence characteristics of composite particles were investigated. The morphological control of (Gd(x)Y(1-x))(2)O(3):Eu particles in spray pyrolysis was also attempted by using colloidal and aqueous solutions. The particles prepared from colloidal solutions containing small amounts of Gd or Y hydroxy carbonate sol as seed material had spherical and filled morphology after the post-treatment at high temperature. On the other hand, the (Gd(x)Y(1-x))(2)O(3):Eu particles prepared from aqueous solutions were hollow and porous after post-treatment in all compositions. Particles prepared from colloidal solutions had photoluminescence emission intensities higher than those of particles prepared from aqueous solutions. Copyright 2000 Academic Press.     

Hydrothermal syntheses and structural characterizations of organic-inorganic hybrid materials of the M(II)-ligand/vanadium oxide system (M(II) = Cu(II) and Zn(II); ligand = 2,2'-bipyridine and 2,2':6',2"-terpyridine)

Investigation into the incorporation of complex transition metal-organic units into vanadium oxide structures has resulted in the preparation of several novel composite materials. Hydrothermal reactions of V(2)O(5), 2,2'-bipyridine, an appropriate Zn or Cu starting material, and H(2)O under a variety of conditions yielded the organic-inorganic hybrid materials [[Zn(2,2'-bpy)](2)V(4)O(12)] (1) and [Cu(2,2'-bpy)V(4)O(10.5)] (2). Blocking an additional coordination site on the secondary metal center by using a tridentate organonitrogen ligand, 2,2':6',2' '-terpyridine in place of 2,2'-bipyridine, allowed the isolation of [Cu(terpy)V(2)O(6)] (3) and [[Zn(terpy)](2)V(6)O(17)] (4). The structure of 1 is a two-dimensional zinc vanadate layer, composed of rings containing four corner-sharing [VO(4)] vanadium(V) tetrahedra linked through six zinc square pyramids, with the 2,2'-bipyridine groups attached to the zinc centers and directed above and below the plane of the layer. In contrast to 1, the layer of 2 is based on a two-dimensional vanadium oxide substructure composed of vanadium(IV) square pyramids and vanadium(V) tetrahedra with copper square pyramids attached through corner-sharing interactions with vanadium tetrahedra such that the bipyridine ligands attached to the copper sites form staggered stacks above and below the plane of the layer. Compound 3 consists of one-dimensional vanadium oxide chains of corner-sharing tetrahedra linked through copper-terpyridine units into a two-dimensional bimetallic oxide of composition [CuV(2)O(6)], while the layer structure of 4 contains more complex one-dimensional vanadium oxide chains composed of fused rings of six corner-sharing vanadium oxide tetrahedra which are linked into a layer through [Zn(terpy)](2+) units.