Al2O3X(X=H,D,T)的电子振动近似理论方法研究

用密度泛函理论(DFT)方法在6-311 G(d,p)水平上对Al2O3X(X=H,D,T)分子较低能量的几何构型进行了优化.计算结果表明该分子有两个可能基态,即Al2O3X(X=H,D,T)(2A′)Cs和Al2O3X(X=H,D,T)(2B2)C2v.全电子计算了氢同位素分子及Al2O3X(X=H,D,T)的能量E、定容热容CV和熵S.应用电子振动近似理论,即用单个分子Al2O3X(X=H,D,T)中的电子和振动能量和熵近似代表它们处于固态时的能量和熵,计算得到固体Al2O3的氢化热力学函数ΔH0,ΔS0,ΔG0以及平衡压力与温度的关系.当Al2O3吸附氢(氘,氚)形成C2v对称性气态Al2O3X(X=H,D,T)对应的固体时,氢气可以排代氘气,氘气可以排代氚气.这种排代效应非常不明显;形成Cs对称性气态Al2O3X(X=H,D,T)对应的固体时,反应的氢氘氚排代效应的顺序为氚排代氘,氘排代氢,与钛等的氢氘氚排代效应的顺序相反.总体而言,这种排代效应都非常弱.随着温度的增加,这一系列反应的氢氘氚排代效应趋于消失.     

A12O3X2（X=H，D，T）的电子振动近似方法

用密度泛函理论在B3LYP／6．311＋＋g（d,P）基组水平上对A12O3X2（X=H,D,T）分子的可能较低能量构型进行了几何优化．结果表明该分子的基态电子态和对称性为A12O3X2（X=H,D,T）（1A’）G,计算了氢同位素分子及A12O3X2（X=H,D,T）的电子能量E、定容热容Cv和熵S．用电子振动近似方法计算了固体A12O3的氢化热力学函数△H0,△S0,△G0,以及平衡压力与温度的关系．当A1203吸附氢（氘,氚）形成固体时,反应的氢氘氚排代效应的顺序为氚排代氘,氘排代氢,与钛等金属与氢及其同位素反应的氢氘氚排代效应的顺序相反．总体来说,这种排代效应都非常弱．随着温度的增加,这系列反应的氢氘氚排代效应趋于消失．     

Al2O3X2（X=H,D,T）的电子振动近似方法

用密度泛函理论在B3LYP/6-311++g（d,p）基组水平上对Al₂O₃X₂（X=H,D,T）分子的可能较低能量构型进行了几何优化.结果表明该分子的基态电子态和对称性为Al₂O₃X₂（X=H,D,T）（¹A′）C_s,计算了氢同位素分子及Al₂O₃X₂（X=H,D,T）的电子能量E、定容热容C_V和熵S.用电子振动近似方法计算了固体Al₂O₃的氢化热力学函数△H⁰,△S⁰,△G⁰,以及平衡压力与温度的关系.当Al₂O₃吸附氢（氘,氚）形成固体时,反应的氢氘氚排代效应的顺序为氚排代氘,氘排代氢,与钛等金属与氢及其同位素反应的氢氘氚排代效应的顺序相反.总体来说,这种排代效应都非常弱.随着温度的增加,这系列反应的氢氘氚排代效应趋于消失.     

LaNi_5和LaNi_(4 .7)Al_(0 .3)氢化物柱内氢氘间的排代

进行了室温附近LaNi5和LaNi4 .7Al0 .3 两种材料上气 固间氢氘的排代实验。两种材料的排代效果都较好 ,相比之下 ,LaNi5的更优。可以推测 ,在不要求得到高纯氚的情况下 ,都可以用作氚的冷卸载贮存床。初步的理论探讨揭示 ,气 固界面的化学交换反应是产生排代效应的原因 ,宏观交换规律决定排代效果。理想化的塔板理论模型对排代流出曲线的描述是有效和适用的 ,塔板高度是材料排代性能优劣的指标 ,在确定的排代条件下 ,如果塔板高度小于 1.0cm ,应该认为具有较好的排代效果。     

LaNi5和LaNi4.7Al0.3氢化物柱内氢氘间的排代

进行了室温附近LaNi5和LaNi4.7Al0.3两种材料上气-固 间氢氘的排代实验。两种材料的排代效果都较好,相比之下,LaNi5的更优。可以推测, 在不要求得到高纯氚的情况下,都可以用作氚的冷卸载贮存床。初步的理论探讨揭示,气- 固界面的化学交换反应是产生排代效应的原因,宏观交换规律决定排代效果。理想化的塔板 理论模型对排代流出曲线的描述是有效和适用的,塔板高度是材料排代性能优劣的指标,在 确定的排代条件下,如果塔板高度小于1.0 cm,应该认为具有较好的排代效果。     

ClF3O和环氧丙烷反应的理论研究

应用密度泛函理论对 ClF3 O 和环氧丙烷的反应机理进行了研究。在 B3PW91/6-31++G(d ,p )水平上优化了各驻点(反应物、中间体、过渡态和产物)的几何构型,并计算了它们的振动频率和零点振动能。采用 CCSD(T)/6-31++G(d ,p )//B3PW91/6-3l++G(d ,p )单点能计算方法求得各物质的能量,并做零点能校正。计算结果表明,ClF3 O 与 C3 H 6 O 可经过不同的反应路径,引发 C3 H 5 O 自由基和 ClOF2自由基生成环氧丙醇和三氟化氯,其中,位于 ClF3 O 周向位置的 F 原子与 C3 H 6 O 的 C(7)上与 CH 3异侧的 H(9)原子结合的活化能最低,仅15.63 kJ/mo1;ClF3 O 与 C3 H 6 O 反应生成的 C3 H 5 O 自由基和 ClOF2自由基继续反应,经过不同反应路径生成 C3 H 4 O、ClOF 和 HF,其中,ClOF2中的 F 原子和 C3 H 5 O 中的 H(2)或 H(4)原子结合是无能垒的过程。整个反应的主要路径为 C3 H 6 O+ClF3→O→TS12 P4(C3 H 5 O+HF+ClOF2→) P12(CH 2 CHCHO+2 HF+ClOF)。     

TiH(D、T)分子性质的量子力学计算

运用量子力学从头计算中的B3LYP密度泛函方法,计算了TiH(D、T)分子的结构,力学,光谱学性质和部分热力学函数,基于Debye晶格振动比热模型和Fermi-Dirac自由电子统计理论,计算了固体Ti的振动内能EV,振动和电子熵SEV,从而最终探讨了Ti吸收氢同位素气体生成一氢化物的ΔH、ΔS、ΔG以及氢同位素的平衡离解压P.结果表明:这些计算方法是可行的;在Ti吸收氢同位素生成一氢化物的反应中,ΔH、ΔS均为负值,且随温度升高,绝对值越大,ΔG则向正的方向增加;Ti的α-β转变对反应的热力学函数变化影响不大;室温直至723K,Ti的一氢同位素化物是相当稳定的;相同温度和压力下,氢置换一氢化物中的氘和氚,以及氘置换氚的反应,在热力学上有利.     

磁约束核聚变研究现状和前景展望

 一、核聚变能是可持续发展最理想的清洁新能源 核聚变可释放出巨大能量。太阳上的巨大能量来源于核聚变反应。氢弹的成功爆炸表明在地球上通过氘氚聚变也可释放出巨大能量。氢的同位素氘存在于海水中,总量十分丰富。     

二溴卡宾与CH3OH多通道反应的理论计算

对单、三重态CBr2与CH3OH的多通道反应进行了理论计算. 在b3lyp/6-311g*水平上优化了势能面上构型并进行了构型确认. 计算了各物种经零点能校正的CCSD(T)能量. 结果表明, 单重态CBr2既可以与O－H键插入生成1,1-二溴代甲醚P1 (CH3OCHBr2), 也可以与C－H键插入生成2, 2-二溴代乙醇P3(Br2HCCH2OH). 同时, 存在单重态CBr2与CH3OH抽提双氢生成Pabs(CH2O+CH2Br2)的反应. 采用统计热力学及Wigner校正的Erying理论研究了主反应通道的热力学及动力学性质, 并对反应通道上的关键点进行了NBO和AIM分析.     

二溴卡宾与CH3OH多通道反应的理论计算

对单、三重态CBr2与CH3OH的多通道反应进行了理论计算. 在b3lyp/6-311g*水平上优化了势能面上构型并进行了构型确认. 计算了各物种经零点能校正的CCSD(T)能量. 结果表明, 单重态CBr2既可以与O－H键插入生成1,1-二溴代甲醚P1 (CH3OCHBr2), 也可以与C－H键插入生成2, 2-二溴代乙醇P3(Br2HCCH2OH). 同时, 存在单重态CBr2与CH3OH抽提双氢生成Pabs(CH2O+CH2Br2)的反应. 采用统计热力学及Wigner校正的Erying理论研究了主反应通道的热力学及动力学性质, 并对反应通道上的关键点进行了NBO和AIM分析.     

A new family of magnetoelectric materials: A2M4O9(A = Ta, Nb; M = Mn, Co)

The existence of the magnetoelectric (ME) effect in the transition metal niobates and tantalates A₂M₄O₉(A = Ta, Nb; M = Mn, Co) has been confirmed by the observation of the electrically induced magnetic moment in these materials. Both parallel and prependicular ME susceptibilities were measured as a function of temperature in powder specimens. The transition temperatures were found to be 110 ±1 (Nb₂Mn₄O₉), 103 ±1 (Ta₂Mn₄O₉), 27.0 ±0.5 (Nb₂Co₄O₉), and 20.6 ±0.5°K (Ta₂Co₄O₉) from the ME measurements.     

Influence of alkali metal superoxides on structure,electronic,and optical properties of Be_(12)O_(12) nanocage:Density functional theory study

The effect of alkali metal superoxides M_3O(M = Li,Na,K) on the electronic and optical properties of a Be_(12)O_(12) nanocage was studied by density functional theory(DFT) and time-dependent density functional theory(TD-DFT).The energy gaps(Eg) of all configurations were calculated.Generally,the adsorption of alkali metal superoxides on the Be_(12)O_(12) nanocage causes a decrease of Eg.Electric dipole moment μ,polarizability α,and static first hyperpolarizability β were calculated and it was shown that the adsorption of alkali metal superoxides on Be_(12)O_(12) increases its polarizability.It was found that the absorption of M_3 O on Be_(12)O_(12) nanocluster improves its nonlinear optical properties.The highest first hyperpolarizability(β≈ 214000 a.u.) is obtained in the K_3O–Be_(12)O_(12)nanocluster.The TD-DFT calculations were performed to investigate the origin of the first hyperpolarizabilities and it was shown that a higher first hyperpolarizability belongs to the structure that has a lower transition energy.     

Structural modulation and physical properties of cobalt-doped layered La_2M_5As_3O_2(M=Cu,Ni) compounds

We investigate the structural variation and physical properties of layered La_2M_5As_3O_2(M=Cu,Ni) compound upon Co doping. It is found that the substitution of Co ion just induces the monotonous change of lattice constants without observing the anomalous kink in superconducting La_2(Cu~(1-x)Nix)_5 As_3O_2 solid-solutions. Meanwhile, this doping barely changes As–As bond length in [M_5As_3]~(2-) subunit(±2%), being significantly smaller than 7% shrinkage of that in La_2(Cu~(1-x)Nix)_5 As_3 O_2. Therefore, the doping dependence of crystal structure exhibits similar trend with Ba~(1-x)K_xFe_2 As_2 without the interference of As1–As 2 bonding, implying that the Co substitution for Cu/Ni is hole-doped. In terms of physical property, La2(Cu1-xCox)~5As_3O_2 turns into itinerant ferromagnetic metal, while La2(Ni1-x Cox)5 As3 O2 shows paramagnetism and suppressed structural phase transition upon Co-doping. The distinct structural variation and absence of superconductivity provide important clues to understand the effect of As–As bond in [M_5 As_3]~(2-) subunit.     

Al,Fe, Mg掺杂Li2MnSiO4的电子结构和电化学性能的第一性原理研究

硅酸锰锂作为锂离子电池正极材料因具有高的理论电容量而一直备受关注, 但其较低的导电率和较差的循环性能阻碍了进一步的发展. 采用第一性原理广义梯度近似GGA+U的方法, 研究了Al, Fe, Mg掺杂Li₂MnSiO₄的电子结构、 脱嵌锂电压和导电性. 研究发现, Al 掺杂的Li₂Mn_0.5Al_0.5SiO₄结构中载流子的数目增加, 电子自旋向上和向下的态密度均穿过费米能级, 呈现金属特性, 提高了体系的导电率. 脱锂Li_xMnSiO₄ (x=1, 0)结构中, 通过计算一次脱锂相结构的形成能得到Al掺杂的一次脱锂结构最稳定, 并且Al掺杂的脱锂相结构体积变化小, 有利于材料循环性能的提高, 同时第一个锂离子脱嵌电压与未掺杂时(4.2 V)相比降低到2.7 V. Fe掺杂降低了Li₂MnSiO₄的带隙, 第一个锂离子脱嵌电压降低到3.7 V. 研究表明, Al的掺杂效果优于Fe和Mg, 更利于硅酸锰锂电化学性质的提高.     

碳硼富勒烯衍生物C18B2M(M=Li,Ti, Fe)的储氢性能计算研究

本文使用密度泛函理论(density functional theory, DFT)中的广义梯度近似(generalized gradient approximation, GGA)研究了经碱金属原子Li、过渡金属原子Ti和Fe原子修饰的富勒烯C₁₈B₂M(M=Li, Ti, Fe)的储氢性能. 研究发现, C₁₈B₂由于B的替代掺杂, 比C₂₀对金属原子具有更高的结合能. 由平均吸附能分析可知: C₁₈B₂Li对H₂的吸附能力较弱, C₁₈B₂Fe对H₂的吸附能力过强, 而C₁₈B₂Ti对H₂的平均吸附能介于0.45-0.59 eV 之间, 介于物理吸附和化学吸附之间 (0.2-0.6 eV), 因此可以实现常温下的可逆储氢. C₁₈B₂M(M=Li, Ti, Fe)能够吸附的H₂数目最多分别为4, 6和4. 由储氢机理分析可知: C₁₈B₂Li主要通过碱金属离子激发的静电场来吸附H₂, 而C₁₈B₂Ti和C₁₈B₂Fe主要通过金属原子与H₂之间的Kubas作用来吸附H₂. 由于C₁₈B₂Ti既有较大的储氢数目, 又可以实现可逆储氢, 因此有望开发成新型纳米储氢材料.     

非晶锂离子导体B2O3-Li2O-LiCl一Al2O3中VO2+的电子自旋共振

两种非晶锂离子导体B₂O₃-0.7Li₂O-0.7LiCl-xAl₂O₃-0.1V₂O₅(x=0.05和0.15)的电子自旋共振谱研究表明:(i)ESR线型是高斯型,证实V₂O₅添加量适当;(ii)超精细结构来源于VO²⁺络离子,具有四角对称性,属C_4v群。越精细耦合张量的平行分量平均值A_//=0.0175cm^-1,垂直分量A_⊥=0.0063cm^-1。由g_//(g_⊥)求出其基态²B_2g与第一激发态²E_g的能级间距△₁=2.46×10⁴ cm^-1,基态与第二激发态²B_1g的能级间距△₂=3.03×10⁴ cm^-1;(iii)变温实验证实:Al₂O₃组分较少(x=0.05)的非晶ESR强度比x=0.15的非晶高3倍至2倍,而Al₂O₃组分越多则ESR强度随温升下降越小。     

Hamiltonian circle actions on symplectic manifolds and the signature

Let M be a symplectic manifold with a Hamiltonian circle action with isolated fixed points. We prove that σ (M) = b₀(M) − b₂(M) + b₄(M) − b₆(M) + … where σ (M) is the signature of M and b_i(M) is the ith Betti number of M.     

Shape coexistence in 76Se within the neutron–proton interacting boson model

We have investigated the low-lying energy spectrum and electromagnetic transition strengths in even–even ⁷⁶Se using the proton–neutron interacting boson model (IBM-2). The theoretical calculation for the energy levels and E2 and M1 transition strengths is in good agreement with the experimental data. Specifically, the excitation energy and E2 transition of ${0}_{2}^{+}$ state, which is intimately associated with shape coexistence, can be accurately reproduced. The analysis on low-lying states and the key structure indicators R₁, R₂, R₃ and R₄ and M1 transitions indicates that there is a coexistence between spherical shape and γ-soft shape in ⁷⁶Se.     

KLL and LMM Auger peak intensity ratio dependence on bond ionicity

A study of the influence of element bond ionicity on ratios shows that a decrease of the ratios of the KL₂₃L₂₃ to KL₁L₂₃, L₂₃M₂₃M₂₃ to L₂₃M₁M₂₃, and L₂₃M₂₃M₂₃ to L₃M₂₃M₄₅ peak intensities occurs with an increase in the effective negative charge of the atom. These dependences are explained by decreasing spatial separation of the 2s and 2p, 3s and 3p, and 3p and 3d electrons. The decreasing spatial separation of the 2s and 2p and the 3p and 3d electrons with increase of the atom effective negative charge becomes less abrupt with increasing element atomic number.     

A study on the nonstoichiometry of tin oxides by coulometric titration

In this investigation, nonstoichiometries and defect structures of tin oxides were studied between 694 and 990 K by coulometric titration using solid state electrolyte (YSZ) cells. The relationship between nonstoichiometry of the oxide (x) and equilibrium oxygen partial pressure (P_o2) was expressed by the proportionality: xP_O2^−1/6. An intermediate oxide phase, Sn₃O₄ between Sn and SnO₂ was observed in the temperature range of 696–732 K. The standard Gibbs energy of formation of Sn₃O₄ via the reaction; was found to be ΔG^o_Sn3O4 = −1163960+417.36 T (J/mol). The standard Gibbs energy change for the defect formation reaction in SnO_2−x was calculated to be ΔG^o_SnO2−x = 3.05×10⁵−38.97 T (J/mol)).