铅锡合金在硫酸溶液中生长阳极Pb(Ⅱ)氧化物膜的机理

用交流阻抗、开路电位衰退及线性电位扫描等方法在0.9V(vs.Hg/Hg₂SO₄)和4.5mol/LH₂SO₄溶液中,研究了铅及Pb-Sn合金电极上所生长的阳极氧化物膜.实验结果表明,阳极膜由溶解-沉淀机理控制生长,膜中微粒间为液膜,借助液膜作为离子通道可使膜中微粒发生阳极反应,锡有利于膜中PbO微粒表层阳极氧化为PbO^1+x(0相似文献   

CO在Sm/Rh(100)模型表面上的吸附与反应

应用AES,LEED,XPS和TDS研究了Rh(100)上Sm膜和Sm/Rh表面合金以及CO在这两类模型表面的吸附与反应.室温下Sm在Rh(100)上的生长遵从SK模式,Sm膜经900K高温退火后可形成有序表面合金.在室温制备的Sm膜/Rh(100)表面上,室温下CO在Sm上的吸附改变了表面结构,生成SmOx和表面碳.随着Sm覆盖度的增加,低温脱附峰(α-CO)面积迅速下降,且峰温向高温方向位移;表明Sm的空间位阻和电子效应同时起作用.在Sm/Rh合金表面上,CO在约590K出现新的脱附峰,可归属为受Sm电正性修饰的Rh原子上的CO脱附峰     

Ni/CeO2-Al2O3催化剂上CH4-CO2转化积炭性能的研究

采用脉冲微量反应技术研究了添加n型半导体氧化物CeO₂对Ni基催化剂上CH₄积炭/CO₂消炭性能的影响,用TPR,XPS和氢吸附技术对催化剂进行了表征.结果表明,活性金属原子Ni与半导体氧化物CeO₂之间存在金属-半导体相互作用(MScI),CeO₂的添加提高了活性原子Ni⁰的d电子密度,在一定程度上抑制了CH₄分子中C-Hσ电子向d轨道的迁移,降低了CH₄裂解积炭活性;可加强Ni⁰原子d轨道向CO₂空反键π轨道的电子迁移,促进CO₂分子的活化,提高CO₂的消炭活性,使Ni/CeO₂-Al₂O₃催化剂具有较强的抗积炭性能.     

铈降低在硫酸溶液中生长的阳极Pb(II)氧化物膜的电阻的研究

应用电化学阻抗频谱法、线性电位扫描法和光电流技术研究了在4.5 mol· dm~(-3) H_2SO_4溶液中Pb-1%(at.)Ce（简称Pb-1Ce）合金在0.9 V (vs. Hg/Hg_2SO_4电极)生长的阳极Pb(II)氧化物膜的电阻较纯铅的低的原因。实验结 果表明,Ce阻抑阳极Pb(II)氧化物膜的生长并增加其孔率,从而降低其电阻。     

一种新型铅钐锡正极板栅合金

目前,铅钙锡合金已广泛用作阀控式铅酸蓄电池(VRLAB)的板栅材料.由于钙的存在,使铅钙锡合金阳极氧化时易形成高阻抗的阳极腐蚀层,并出现晶间腐蚀,电池循环充放电能力仍不理想.为克服铅钙锡合金作为正极板栅材料的不利因素.     

掺碳球形Ni(OH)2的特性

电子导电剂;充放电特性;掺碳球形Ni(OH)2的特性     

贮氢合金电极在葡萄糖电化学还原中的应用(英文)

以贮氢合金电极作催化还原电极,恒电位电解葡萄糖,发现合金经表面处理及电极的活化后,即可提高电流效率,在最优条件下,电解葡萄糖制山梨醇电流效率高达90%,葡萄糖转化率达80%以上.测试了电极的使用寿命,同时对电极中毒及再生方法进行了探讨.     

铁铬合金空蚀过程的研究

研究了4种铁铬合金在氯化钠溶液体系中的空泡腐蚀行为.重点考察合金性能及空泡作用区的相对面积对合金空蚀损失量的影响.结果表明:合金空蚀损失量随空泡作用区与非空泡作用区表面面积比的增大而增加;合金的耐蚀性和机械性能同时影响其空蚀损失量.     

Phase transition and pitting corrosion behaviour for Mo—implanted aluminium

Molybdenum ions are implanted into aluminium with high ion flux and high dose at elevated temperatures of 200℃, 400℃ and 500℃. Due to the high temperature and high flux of vacancies and interstitial atoms, the atom diffusion and chemical effects are enhanced during the ion implantation. The effects increase with increasing ion flux and dose, so that new phase formation and phase transition emerge noticeably. X-ray diffraction analysis shows that when the aluminium is implanted with Mo ions at a low ion flux (25μA/cm²), the Al₅Mo alloy is formed. The atomic ratio of Mo/Al of the Al₅Mo phase is close to 20%. When the aluminium is implanted with Mo ions at a high ion flux (50μA/cm²), the phase transition from Al₅Mo to Al₁₂Mo appears, and the latter is dominant, which is determined to be the final phase. The ratio of Mo/Al in Al₁₂Mo is 7.7%. Rutherford backscattering spectroscopy indicates also that the Mo/Al atom ratio is ～7% to ～8% in Mo-implanted aluminium. The atomic ratios of the constituents in Al₅Mo and Al₁₂Mo are of stoichiometric composition for these alloys. The thicknesses of the Al₁₂Mo alloy layers for Mo-implanted Al with ion doses of 3×10¹⁷/cm² and 1×10¹⁸/cm² are 550nm and 2000nm, respectively. The pitting corrosion potential V_p increases obviously. It is clear that due to the formation of Al₁₂Mo alloy layer, the pitting corrosion resistance is enhanced.     

Stacking fault energy of cryogenic austenitic steels

Stacking fault energy and stacking fault nucleation energy are defined in terms of the physical nature of stacking faults and stacking fault energy, and the measuring basis for stacking fault energy. Large quantities of experimental results are processed with the aid of a computer and an expression for calculating stacking fault energy has been obtained as γ³⁰⁰_SF(mJ·m^-2)=γ⁰_SF+1.59Ni-1.34Mn+0.06Mn²-1.75Cr+0.01Cr²+15.21Mo-5.59Si-60.69(C+1.2N)^1/2 + 26.27(C+1.2N)(Cr+Mn+Mo)^1/2+0.61[Ni·(Cr+Mn)]^1/2.