MoO3和SiO2掺杂对Ce0.8Nd0.2O1.9固体电解质结构和导电性能的影响

采用溶胶-凝胶法合成高纯(<50 mg·kg-1 SiO2)Ce0.8Nd0.2O1.9(NDC)和SiO2含量为500 mg·kg-1的Ce0.8Nd0.2O1.9(NDCSi)体系,将1mol%MoO3分别加入到NDC和NDCSi体系,比较研究MoO3掺杂对体系微观结构和电性能的影响。通过X射线衍射(XRD)和场发射扫描电子显微镜(FE-SEM)对材料进行表征,交流阻抗(AC)分析仪测试材料的电阻。结果表明:MoO3和SiO2的加入均没有破坏体系的立方莹石结构;MoO3掺杂能提高NDC和NDCSi陶瓷材料的致密度,提高其晶界电导率和总电导率;MoO3掺入NDC体系具有烧结助剂的作用,掺入NDCSi体系既具有烧结助剂的作用,又具有晶界改善剂的作用。     

MgO掺杂Ce_(0.9)Sm_(0.1)O_(2-δ)固体电解质的结构和电性能

采用溶胶-凝胶法合成SiO2含量为5.0×10-4(w)的Ce0.9Sm0.1O2-δ(SDC)粉体(SDCSi),并将0-3.0%(x)MgO分别加入到SDCSi陶瓷粉体中,用X射线衍射(XRD)和场发射扫描电子显微镜(FE-SEM)对材料进行表征,用交流阻抗谱(AC)测试材料的电性能.结果表明:MgO掺杂能使SDCSi的烧结温度降低100-200℃,提高陶瓷材料的致密度;清除或降低陶瓷材料晶界处SiO2杂质的有害影响,显著提高晶粒/晶界电导率和总电率;MgO掺杂到SDCSi具有烧结助剂和晶界杂质清除剂的双重作用.     

Fe2O3掺杂Ce0.8Nd0.2O1.9固体电解质的结构与导电性能

采用溶胶-凝胶法合成SiO2含量小于50×10-6的Ce0.8Nd0.2O1.9(NDC)陶瓷粉体,并将少量Fe2O3加入到NDC体系中,讨论Fe2O3的掺杂对其微观结构及电性能的影响。通过X射线衍射(XRD)等手段对氧化物进行结构表征,交流阻抗谱(AC)测试电性能。研究表明,Fe2O3的掺杂显著提高NDC陶瓷材料的致密度;相比于NDC而言,加入Fe2O3后材料的晶界电导率提高约12倍,总电导率提高约6倍。     

Ce_(0.8)Nd_(0.2)O_(1.9)-La_(0.95)Sr_(0.05)Ga_(0.9)Mg_(0.1)O_(3-δ)固体复合电解质的结构和电性能

采用溶胶-凝胶法分别制备La0.95Sr0.05Ga0.9Mg0.1O3-δ(LSGM)和Ce0.8Nd0.2O1.9(NDC)电解质,并在NDC溶胶中加入0-15%(w,质量分数)的LSGM预烧粉体制得NDC-LSGM复合电解质,研究不同质量比复合电解质的结构和电性能.采用X射线衍射(XRD)、场发射扫描电子显微镜(FE-SEM)和X能量色散谱仪(EDS)对样品进行结构表征,交流(AC)阻抗谱测试样品导电性能.结果表明:NDC-LSGM复合体系主要由立方萤石结构相、钙钛矿结构相和杂质相组成;LSGM的添加可促进晶粒的生长,产生大量相界面,清除或降低SiO2有害影响,明显提高晶界导电性;LSGM质量分数为10%的样品NL10具有最高晶界电导率和总电导率,400°C时NL10的晶界电导率σgb和总电导率σt分别为12.15×10-4和3.49×10-4S cm-1,与NDC的σgb(1.41×10-4S cm-1)和σt(1.20×10-4S cm-1)相比分别提高了7.62和1.91倍,总电导率的提高主要归因于晶界电导率的影响.     

La1-xSrxCu0.9Fe0.1O2.5-δ阴极材料的合成与电导率研究

采用低温燃烧合成技术制备了Lal-xSrxCu0.9Fe0.1O2.5-δ(x=0.1-0.4)粉体。利用X-射线衍射(XRD)和差热分析(DTA)技术对粉体的性能进行了表征。XRD结果表明,经800℃焙烧的La0.9Sr0.1Cu0.9Fe0.1O2.5-δ粉体的对称性较低,未形成钙钛矿结构,其余Lal-xSrxCu0.9Fe0.1O2.5-δ(x=0.2-0.4)粉体为四方钙钛矿结构,晶体结构参数之间满足关系式a=b≈2(2c)~(1/2)。DTA结果证明Lal-xSrxCu0.9Fe0.1O2.5-δ在800℃以下是热力学稳定的,不会发生分解反应。采用直流四电极法测试了Lal-xSrxCu0.9Fe0.1O2.5-δ试样在100—800℃之间的电导率。试样的电导率~(ln(σT)与1/T之间呈很好的线性关系,说明Lal-xSrxCu_(0.9)Fe0.1O2.5-δ在测试温度范围内服从小极化子导电机制。Sr掺杂量对试样的电导率和电导活化能有着明显的影响,当Sr掺杂量为0.3时,Lal-xSrxCu0.9Fe0.1O2.5-δ的电导率最高,电导活化能最小。     

Ce_(1-x)Sc_xO_(2-x/2)固体电解质的微观结构及电性能研究

研究了Sc_2O_3掺杂CeO_2基电解质材料的微观形貌和电性能。采用溶胶凝胶法制备了Sc_2O_3掺杂CeO_2基电解质粉体, Sc_2O_3掺杂量分别为6%, 8%, 10%。采用单向压力法将电解质粉体压制为圆片状素坯,分别在1400, 1450, 1500℃下,空气中烧结制备电解质材料。研究分析了不同掺杂比例及不同烧结温度对电解质的相组成、微观形貌及电导率的影响。实验结果表明:低温下, Sc_2O_3能溶于CeO_2中形成固溶体,随着Sc_2O_3掺杂量由6%增加到10%(摩尔分数,下同),晶胞参数减小;高温烧结时溶于CeO_2中的Sc_2O_3会析出,且随着烧结温度的升高析出量增加;当Sc_2O_3掺杂量为8%、烧结温度为1500℃时,在750℃时Sc_2O_3掺杂CeO_2电解质电导率最大为8.78×10~(-3) S·cm~(-1),活化能为1.220 eV。     

掺杂MoO_3对Ce_(0.8)Nd_(0.2)O_(1.9)固体电解质结构与电性能的影响

采用溶胶凝胶方法将过渡金属氧化物MoO3加入到Ce0.8Nd0.2O1.9体系中,讨论MoO3的掺杂对微观结构及电性能的影响。通过X-射线衍射(XRD)、场发射扫描电镜(FE-SEM)等手段对氧化物进行结构表征,交流阻抗谱测试电性能。结果表明:烧结过程中MoO3在晶粒边缘形成液相,增加了晶粒间浸润性,晶粒间位置重排并接触,晶界滑移加快,促使材料致密化,晶界体积分数降低;总电导率和晶界电导率因晶界电阻减少而提高。600℃时,NDC的σt和σgb分别为6.42×10-3和2.03×10-2S·cm-1,加入MoO3后材料的σt提高约1.5倍,σgb提高约4倍。MoO3是NDC体系理想的烧结助剂。     

Al掺杂La10(SiO4)6O3的制备及其导电性能

以溶胶-凝胶法在850℃制备了Al掺杂La10(SiO4)6O3,即La10(SiO4)6-x(AlO4)xO3-0.5x(x=0,0.5,1.0,1.5和2.0),通过TG-DTA、XRD、IR和SEM表征,所得产品为磷灰石相。以电化学阻抗谱研究了其导电性能,发现决定电导率大小的因素有两种,一是间隙氧的数量,二是晶胞的大小,两种因素的综合作用,使得Al掺杂0.5时La10(SiO4)5.5(AlO4)0.5O2.75的电导率最大,在700℃时其电导率达到1.88×10-2S·cm-1。氧分压对电导率的研究表明,其主要的电荷载体是O2-离子。     

La2O3对氧化铝透明陶瓷显微结构和透光性能的影响

采用传统无压烧结工艺在氢气氛下制备Al2O3透明陶瓷。实验结果表明：MgO和La2O3复合添加时，随着La2O3掺杂量的增加体积密度总体上保持上升的趋势。随着保温时间的延长，陶瓷的致密化程度增大，残余气孔逐步排出，晶粒进一步长大。采用La2O3和MgO复合添加比单独掺入MgO陶瓷样品透过率更高，掺杂效果更好。在烧结温度为1750℃，保温时问为1h条件下，在波艮为300～800nm测试范围内，陶瓷样品的全透过率大于82％，最大值为86％。     

中温固体氧化物燃料电池复合阴极Pr0.6-zSr0.4Co0.8Fe0.2O3-δ-SDC性能研究

采用改进的溶胶-凝胶法合成固体氧化物燃料电池阴极系粉体Pr0.6-zSr0.4Co0.8Fe0.2O3-δ(PSCF)(z=0,0.02,0.05,0.1)。使用X射线衍射(XRD)、扫描电子显微镜(SEM)对其相结构与形貌进行了分析,结果表明:900℃以上焙烧后的阴极粉体Pr0.6-zSr0.4Co0.8Fe0.2O3-δ(z=0,0.02,0.05,0.1)为单一的钙钛矿结构。1000℃烧结的样品内粒子分布比较均匀,且颗粒内部存在一定程度的空隙,并与电解质附着情况良好。用直流四电极法测试阴极体系样品在400～750℃的电导率,发现各试样混合离子电子电导率均高于786 S.cm-1,能够满足固体氧化物燃料电池对阴极电导率的要求。用交流阻抗法测定PSCF-Ce0.8Sm0.2O1.9体系样品的阻抗谱,得到1000℃烧结的阴极体系对称电池在测试温度为750℃z=0,z=0.02,z=0.05时的极化电阻分别为0.041,0.040,0.034Ω.cm-2。     

A kinetic study of the reactions FeO+ + O, Fe+.N2 + O, Fe+.O2 + O and FeO+ + CO: implications for sporadic E layers in the upper atmosphere

These gas-phase reactions were studied by pulsed laser ablation of an iron target to produce Fe(+) in a fast flow tube, with detection of the ions by quadrupole mass spectrometry. Fe(+).N(2) and Fe(+).O(2) were produced by injecting N(2) and O(2), respectively, into the flow tube. FeO(+) was produced from Fe(+) by addition of N(2)O, or by ligand-switching from Fe(+).N(2) following the addition of atomic O. The following rate coefficients were measured: k(FeO(+) + O --> Fe(+) + O(2), 186-294 K) = (3.2 +/- 1.5) x 10(-11); k(Fe(+).N(2) + O --> FeO(+)+ N(2), 294 K) = (4.6 +/- 2.5) x 10(-10); k(Fe(+).O(2) + O --> FeO(+) + O(2), 294 K) = (6.3 +/- 2.7) x 10(-11); and k(FeO(+) + CO --> Fe(+) + CO(2), 294 K) = (1.59 +/- 0.34) x 10(-10) cm(3) molecule(-1) s(-1), where the quoted uncertainties are a combination of the 1sigma standard errors in the kinetic data and the systematic experimental errors. The surprisingly slow reaction between FeO(+) and O is examined using ab initio quantum calculations of the relevant potential energy surfaces. The importance of this reaction for controlling the lifetime of sporadic E layers is then demonstrated using a model of the upper mesosphere and lower thermosphere.     

A kinetic study of Mg+ and Mg-containing ions reacting with O3, O2, N2, CO2, N2O and H2O: implications for magnesium ion chemistry in the upper atmosphere

Reactions between Mg(+) and O(3), O(2), N(2), CO(2) and N(2)O were studied using the pulsed laser photo-dissociation at 193 nm of Mg(C(5)H(7)O(2))(2) vapour, followed by time-resolved laser-induced fluorescence of Mg(+) at 279.6 nm (Mg(+)(3(2)P(3/2)-3(2)S(1/2))). The rate coefficient for the reaction Mg(+) + O(3) is at the Langevin capture rate coefficient and independent of temperature, k(190-340 K) = (1.17 ± 0.19) × 10(-9) cm(3) molecule(-1) s(-1) (1σ error). The reaction MgO(+) + O(3) is also fast, k(295 K) = (8.5 ± 1.5) × 10(-10) cm(3) molecule(-1) s(-1), and produces Mg(+) + 2O(2) with a branching ratio of (0.35 ± 0.21), the major channel forming MgO(2)(+) + O(2). Rate data for Mg(+) recombination reactions yielded the following low-pressure limiting rate coefficients: k(Mg(+) + N(2)) = 2.7 × 10(-31) (T/300 K)(-1.88); k(Mg(+) + O(2)) = 4.1 × 10(-31) (T/300 K)(-1.65); k(Mg(+) + CO(2)) = 7.3 × 10(-30) (T/300 K)(-1.59); k(Mg(+) + N(2)O) = 1.9 × 10(-30) (T/300 K)(-2.51) cm(6) molecule(-2) s(-1), with 1σ errors of ±15%. Reactions involving molecular Mg-containing ions were then studied at 295 K by the pulsed laser ablation of a magnesite target in a fast flow tube, with mass spectrometric detection. Rate coefficients for the following ligand-switching reactions were measured: k(Mg(+)·CO(2) + H(2)O → Mg(+)·H(2)O + CO(2)) = (5.1 ± 0.9) × 10(-11); k(MgO(2)(+) + H(2)O → Mg(+)·H(2)O + O(2)) = (1.9 ± 0.6) × 10(-11); k(Mg(+)·N(2) + O(2)→ Mg(+)·O(2) + N(2)) = (3.5 ± 1.5) × 10(-12) cm(3) molecule(-1) s(-1). Low-pressure limiting rate coefficients were obtained for the following recombination reactions in He: k(MgO(2)(+) + O(2)) = 9.0 × 10(-30) (T/300 K)(-3.80); k(Mg(+)·CO(2) + CO(2)) = 2.3 × 10(-29) (T/300 K)(-5.08); k(Mg(+)·H(2)O + H(2)O) = 3.0 × 10(-28) (T/300 K)(-3.96); k(MgO(2)(+) + N(2)) = 4.7 × 10(-30) (T/300 K)(-3.75); k(MgO(2)(+) + CO(2)) = 6.6 × 10(-29) (T/300 K)(-4.18); k(Mg(+)·H(2)O + O(2)) = 1.2 × 10(-27) (T/300 K)(-4.13) cm(6) molecule(-2) s(-1). The implications of these results for magnesium ion chemistry in the atmosphere are discussed.     

氧化铟掺杂对ZnFe2O4半导体气敏性能的影响

用化学共沉淀法在ＺｎＦｅ２Ｏ４中掺入Ｉｎ２Ｏ３．Ｘ射线衍射分析证实，Ｉｎ２Ｏ３与ＺｎＦｅ２Ｏ３之间没有新相生成，晶格常数有微小变化．掺入Ｉｎ２Ｏ３降低了ＺｎＦｅ２Ｏ４的电导，改变了该系列材料的导电机制，提高了材料对乙醇的敏感性和选择性，而且缩短了材料的响应时间     

Lowering grain boundary resistance of BaZr(0.8)Y(0.2)O(3-δ) with LiNO3 sintering-aid improves proton conductivity for fuel cell operation

A novel sintering additive based on LiNO(3) was used to overcome the drawbacks of poor sinterability and low grain boundary conductivity in BaZr(0.8)Y(0.2)O(3-δ) (BZY20) protonic conductors. The Li-additive totally evaporated during the sintering process at 1600 °C for 6 h, which led to highly dense BZY20 pellets (96.5% of the theoretical value). The proton conductivity values of BZY20 with Li sintering-aid were significantly larger than the values reported for BZY sintered with other metal oxides, due to the fast proton transport in the "clean" grain boundaries and grain interior. The total conductivity of BZY20-Li in wet Ar was 4.45 × 10(-3) S cm(-1) at 600 °C. Based on the improved sinterability, anode-supported fuel cells with 25 μm-thick BZY20-Li electrolyte membranes were fabricated by a co-firing technique. The peak power density obtained at 700 °C for a BZY-Ni/BZY20-Li/La(0.6)Sr(0.4)Co(0.2)Fe(0.8)O(3-δ) (LSCF)-BZY cell was 53 mW cm(-2), which is significantly larger than the values reported for fuel cells using electrolytes made of BZY sintered with the addition of ZnO and CuO, confirming the advantage of using Li as a sintering aid.     

O2(a1Δg) + Mg, Fe, and Ca: experimental kinetics and formulation of a weak collision, multiwell master equation with spin-hopping

The first excited electronic state of molecular oxygen, O(2)(a(1)Δ(g)), is formed in the upper atmosphere by the photolysis of O(3). Its lifetime is over 70 min above 75 km, so that during the day its concentration is about 30 times greater than that of O(3). In order to explore its potential reactivity with atmospheric constituents produced by meteoric ablation, the reactions of Mg, Fe, and Ca with O(2)(a) were studied in a fast flow tube, where the metal atoms were produced either by thermal evaporation (Ca and Mg) or by pulsed laser ablation of a metal target (Fe), and detected by laser induced fluorescence spectroscopy. O(2)(a) was produced by bubbling a flow of Cl(2) through chilled alkaline H(2)O(2), and its absolute concentration determined from its optical emission at 1270 nm (O(2)(a(1)Δ(g) - X(3)Σ(g) (-)). The following results were obtained at 296 K: k(Mg + O(2)(a) + N(2) → MgO(2) + N(2)) = (1.8 ± 0.2) × 10(-30) cm(6) molecule(-2) s(-1); k(Fe + O(2)(a) → FeO + O) = (1.1 ± 0.1) × 10(-13) cm(3) molecule(-1) s(-1); k(Ca + O(2)(a) + N(2) → CaO(2) + N(2)) = (2.9 ± 0.2) × 10(-28) cm(6) molecule(-2) s(-1); and k(Ca + O(2)(a) → CaO + O) = (2.7 ± 1.0) × 10(-12) cm(3) molecule(-1) s(-1). The total uncertainty in these rate coefficients, which mostly arises from the systematic uncertainty in the O(2)(a) concentration, is estimated to be ±40%. Mg + O(2)(a) occurs exclusively by association on the singlet surface, producing MgO(2)((1)A(1)), with a pressure dependent rate coefficient. Fe + O(2)(a), on the other hand, shows pressure independent kinetics. FeO + O is produced with a probability of only ～0.1%. There is no evidence for an association complex, suggesting that this reaction proceeds mostly by near-resonant electronic energy transfer to Fe(a(5)F) + O(2)(X). The reaction of Ca + O(2)(a) occurs in an intermediate regime with two competing pressure dependent channels: (1) a recombination to produce CaO(2)((1)A(1)), and (2) a singlet∕triplet non-adiabatic hopping channel leading to CaO + O((3)P). In order to interpret the Ca + O(2)(a) results, we utilized density functional theory along with multireference and explicitly correlated CCSD(T)-F12 electronic structure calculations to examine the lowest lying singlet and triplet surfaces. In addition to mapping stationary points, we used a genetic algorithm to locate minimum energy crossing points between the two surfaces. Simulations of the Ca + O(2)(a) kinetics were then carried out using a combination of both standard and non-adiabatic Rice-Ramsperger-Kassel-Marcus (RRKM) theory implemented within a weak collision, multiwell master equation model. In terms of atmospheric significance, only in the case of Ca does reaction with O(2)(a) compete with O(3) during the daytime between 85 and 110 km.     

可见光下Fe3+掺杂对K2La2Ti3O10分解水制氢性能的影响

采用溶胶-凝胶法制备了Fe3+掺杂的Fe-K2La2Ti3O10光催化剂, 并通过X射线衍射(XRD)、紫外-可见漫反射(DRS)、X射线光电子能谱(XPS)等技术对其进行了表征和分析, 考察了不同掺杂量对K2La2Ti3O10的性质及光催化分解水制氢活性的影响. 结果表明, Fe-K2La2Ti3O10在400-650 nm范围内显示强吸收, 光谱响应扩展到可见光区(λ>400 nm), 掺杂Fe3+后, K2La2Ti3O10的可见光区的光催化制氢活性显著提高, 掺杂量为nFe/nTi=0.04时活性最佳, 当催化剂用量为0.1 g, 反应液为CH3OH(30 mL)+H2O(90 mL)时, 产氢量达到1.92 μmol·h-1, 为未掺杂时的4倍.     

La0.5>RE0.3Sr0.2FeO3－δ (RE = Nd、Ce、Sm)体系双稀土阴极材料的制备与电性能

采用甘氨酸-硝酸盐法(GNP)合成了La0.5RE0.3Sr0.2FeO3－δ(RE=Nd、Ce、Sm)系列复合氧化物粉体. 用X射线衍射(XRD)和TG-DSC分析了样品钙钛矿物相的形成过程, 用Archimedes排水法测量体积密度并计算烧结样品的相对密度, 用四端子技术测量电导率. 结果显示, 掺Nd的样品1200 ℃烧结2 h成为单一立方钙钛矿结构, 掺Ce样品有明显的CeO2立方相析出, 掺Sm样品主相为钙钛矿结构伴有微弱的杂峰. 1250 ℃烧结2 h的La0.5Nd0.3Sr0.2FeO3－δ在600 ℃时电导率高达100 S•cm-1以上, 明显高于La0.5Ce0.3Sr0.2FeO3－δ及La0.5Sm0.3Sr0.2FeO3－δ样品的电导率, 预示着La0.5Nd0.3Sr0.2FeO3－δ可能是一种良好的中温固体氧化物燃料电池(SOFC)阴极材料.     

纳米氧化铁修饰玻碳电极检测痕量镉离子

制备了一种纳米氧化铁修饰玻碳电极,并研究了镉离子在该修饰电极上的溶出伏安行为。结果表明,纳米氧化铁颗粒能有效促进镉离子的溶出伏安响应。在pH 6.0的磷酸缓冲溶液中,镉离子能有效吸附在纳米氧化铁表面并在-1.0 V时被还原。被还原的镉在正向扫描过程中可以重新氧化,并在-0.85 V处出现一明显的溶出伏安氧化峰。该峰电流随镉离子浓度的增大而增大,可用于对镉离子的检测。在最佳检测条件(pH 6.0,富集时间350 s,富集电位-1.0 V)下,镉离子的响应电流与其浓度在6.0×10-10～1.0×10-8mol/L以及1.0×10-8～1.0×10-5 mol/L范围内呈良好线性,检出限(S/N=3)为1.0×10-10 mol/L。干扰实验结果表明,一些常见的阳离子以及阴离子对镉离子的检测无明显干扰。将该方法用于实际样品的检测,回收率良好。