溶胶-凝胶法制备Y2Zr2O7∶Tm3+及其发光性能研究

以柠檬酸为络合剂采用溶胶-凝胶法制备了（Y1-xTmx）2Zr2O7（x=0.005,0.01,0.03,0.05）荧光粉.采用X-射线衍射分析仪（XRD）、扫描电子显微镜（SEM）和荧光光谱仪分别检测了Y2Zr2O7∶Tm3+的晶体结构、颗粒形貌以及样品的荧光光谱.XRD图谱表明,所得到的产物Y2Zr2O7∶Tm3+为单一相的萤石结构,而且Tm3+的掺杂并没有改变其晶体结构.荧光光谱的测试表明,在359 nm波长的紫外光激发下,1000℃下烧结的（Y1-xTmx）2Zr2O7（x=0.01）样品的发光性能最好,发射峰对应于Tm3+的1D2→3F4跃迁和1G4→3H6跃迁,并对其发光机理进行了探讨.样品在454 nm处的发光强度随Tm3+离子掺杂浓度的增加先升高后降低,即出现了浓度猝灭的现象,当Tm3+掺杂浓度摩尔百分比为1%时,样品的发光强度达到最大.     

干熄焦除尘灰配入钒钛矿烧结的研究

烧结固体燃料中配加一定量的干熄焦除尘灰,在保证烧结过程主要参数和烧结矿指标变化不大的前提下,可以适当降低烧结矿固体燃料消耗和生产成本。对干熄焦除尘灰配入钒钛矿烧结固体燃料的可行性及其合理配比进行了探讨,认为干熄焦除尘灰配入钒钛矿烧结是可行的,且配比在0.2%较为适宜。     

精密锻造技术的研究进展与发展趋势

热精密锻造技术不仅能赋予零件近净复杂形状和尺寸,而且能使零件宏观性能在坯料性能基础上得到提高,是少无废料产生、绿色、节约型的高效高性能制造技术。综述了热精密锻造技术的应用现状,介绍了热模锻造、等温锻造、基于数值模拟的预制坯优化设计和精密锻造全过程工艺优化设计的国内外研究现状,最后对热精密锻造技术发展方向进行了展望。     

宝钢炼焦节能技术的成效及展望

炼焦作为高能耗、高污染产业,具有巨大的节能减排潜力。结合宝钢炼焦现状,介绍了回收焦炭显热的干熄焦技术,以焦炉废气为载气的蒸汽回转干燥煤调湿技术,新型预制块炉门、炉盖技术等,通过上述技术应用达到了充分利用焦炉显热,节约能源的目的。最后对焦炉荒煤气显热回收、烟道废气余热回收进行了论述与展望。     

发动机气门弹簧断裂失效分析

采用宏微观分析、金相检验、显微硬度检测以及化学成分分析等方法对某汽车发动机气门弹簧的早期断裂原因进行了分析。结果表明:弹簧的断裂属性为疲劳断裂;弹簧钢丝原材料在淬火加热过程中与盐浴炉电极接触造成表面电弧烧伤形成麻坑,是引起该气门弹簧早期疲劳断裂的根本原因。     

双壳微纳米相变胶囊/石膏复合材料等温吸放湿特性及机理研究

为了分析双壳微纳米相变胶囊复合材料的亲水性能,采用饱和盐溶液法对双壳微纳米相变胶囊复合材料的吸放湿平衡含湿量进行测试。并且采用红外光谱仪、扫描电镜对双壳微纳米相变胶囊、双壳微纳米相变胶囊复合材料结构及形貌进行测试。通过数学拟合方法,依据菲克定律以及吸放湿滞回环的表现,发现双壳微纳米相变胶囊复合材料存在着"绑定"水分,并提出了化学吸附不可逆吸放湿机理。结果表明,双壳微纳米相变胶囊外壳高分子壁材在复合材料吸放湿过程中,既有类似石膏孔隙的物理吸附,同时也存在"绑定"水分的化学吸附;"绑定"水分量随双壳微纳米相变胶囊掺量增加而增加,并且不随等温条件下相对湿度改变而变化。     

热处理工艺对合金渗碳钢件加工表面的影响

对20CrMoH低合金钢件分别进行了正火及模仿锻造余温正火处理。对两种试样的显微组织、硬度及加工后的表面变形进行了测量。研究表明,锻造余热正火时获得平衡组织,硬度比正火试样小,且分布均匀,加工后变形量比正火试样小。     

Measurement of phase equilibria in Ti-Ni-Sn system

Phase relations of the Ti-Ni-Sn ternary system were investigated via alloy sampling assisted with X-ray diffractometry (XRD) and electron probe micro-analysis (EPMA). A new binary phase with composition of TiSn₄ (molar fraction, %) was detected at 508 K. In addition, a supplementary phase (Ti_1–x–yNi_xSn_y)Ni₃ (τ, AuCu₃-type) was observed at 873 and 973 K. According to the characterised microscopic structure in various annealed alloys, four ternary phases were detected in Ti-Ni-Sn ternary system: TiNiSn, TiNi₂Sn, Ti₂Ni₂Sn and (Ti_1–x–yNi_xSn_y)Ni₃. Additionally, isothermal sections of Ti-Ni-Sn ternary system at 508, 873 and 973 K were constructed. By comparing three isothermal sections, a peri-eutectic reaction, L+TiNi₂Sn→Ni₃Sn₄+TiNiSn, was deduced, which occurs at a temperature between 873 and 973 K. Furthermore, the solubility of Sn in TiNi and Ni in Ti₅Sn₃ was detected.     

Evolution and distribution of Al2Sm phase in as-extruded AZ61–xSm magnesium alloys during semi-solid isothermal heat-treatment

The evolution and distribution of Al₂Sm phase in as-extruded AZ61–xSm (x=0, 1.5, 2.0 and 2.5, mass fraction, %) magnesium alloys during semi-solid isothermal heat treatment were investigated. The results showed that when as-extruded AZ61 magnesium alloys were modified with Sm, the smaller and rounder grains were obtained during semi-solid isothermal heat treatment. When the Sm content is 2.0% (mass fraction), the average size of the globular grains reached the smallest value of 90 μm. Although a few Al₂Sm particles existed in the α-Mg grains, most of Al₂Sm particles solidified at the edge of the globular grains with the width of ~20 μm. These phenomena are mainly attributed to the forces acting on Al₂Sm particles in front of the solid–liquid interface, leading to Al₂Sm particles accumulating at the solid–liquid interface and then solidifying at the edge of the globular grains in the quenching process.     

Computation of synthetic surface heat transfer coefficient of 7B50 ultra-high-strength aluminum alloy during spray quenching

According to inverse heat transfer theory, the evolutions of synthetic surface heat transfer coefficient (SSHTC) of the quenching surface of 7B50 alloy during water-spray quenching were simulated by the ProCAST software based on accurate cooling curves measured by the modified Jominy specimen and temperature-dependent thermo-physical properties of 7B50 alloy calculated using the JMatPro software. Results show that the average cooling rate at 6 mm from the quenching surface and 420–230 °C (quench sensitive temperature range) is 45.78 °C/s. The peak-value of the SSHTC is 69 kW/(m²·K) obtained at spray quenching for 0.4 s and the corresponding temperature of the quenching surface is 160 °C. In the initial stage of spray quenching, the phenomenon called “temperature plateau” appears on the cooling curve of the quenching surface. The temperature range of this plateau is 160–170 °C with the duration about 3 s. During the temperature plateau, heat transfer mechanism of the quenching surface transforms from nucleate boiling regime to single-phase convective regime.