6to4与ISATAP技术相结合的IPv6网络实现

在IPv4向IPv6过渡期间,多种过渡技术可以互相支持、互相组合使用,以达到互利互助。简要介绍了其中2种隧道技术:6to4技术和ISATAP技术,提出了1种基于两者结合的新型实验网络的实现方案。具体讨论了在Linux下如何组建这种新型实验网络平台,详细阐明了如何配置IPv6主机以及双栈路由器,为IPv4过渡到IPv6提供1个可行的方案。     

基于Pro/E的设计与工艺信息共享关键技术研究

阐述了利用Visual C＋＋6．0、Pro／Toolkit和数据库的强大功能从设计信息中提取相关的零部件信息及将工艺信息输出到绘图环境下的具体方法和过程，实现了在Pro／E环境下设计与工艺之间的信息共享、无缝连接，并给出了实例。     

工艺参数对微区沉淀法制备纳米MgAl2O4粉体的影响

采用高分子网络微区沉淀法制备纳米镁铝尖晶石（MgAl2O4）粉体，并采用TGA／DTA、XRD和TEM等分析测试技术对前驱体的热分解和所制得粉体的物相组成、形貌及颗粒尺寸进行表征，结果表明所制得的MgAl2O4粉体颗粒粒径小，结晶良好，成分单一且粒径大小均匀。而实验过程中工艺参数的改变会对生成粉体的粒径和形貌产生一定的影响，进而即研究了各种工艺参数的改变对该方法制备纳米MgAl2O4粉体的影响。     

一种DCT域的最优均值量化盲图像水印算法

针对常规的图像水印算法不能很好地实现水印不可感知性和鲁棒性折中的问题,给出了一种最优均值量化盲水印算法.该算法首先对水印图像进行Arnold置乱,提高了水印的安全性;然后将载体图像进行8×8分块DCT(离散余弦变换),并根据均值量化原理将置乱后的水印嵌入到局部量化噪声值最小的图像子块中,提高了水印的不可感知性;最后水印提取时可以实现盲提取.实验结果表明,该算法对加噪、剪切、JPEG压缩、滤波等多种攻击都具有很强的鲁棒性.     

非均相催化湿式氧化活性红2BF的研究

以Fe/AC为催化剂、O2为氧化剂的非均相催化氧化体系处理偶氮染料活性红2BF,考察了反应温度、氧分压、废水pH、催化剂投加量等因素对降解效果的影响。结果表明,染料初始质量浓度为400 mg/L时,在温度150℃、氧分压0.5 MPa、pH=3、反应时间60 min、催化剂投加量为4 g/L的最佳条件下,活性红2BF色度几乎完全去除,TOC去除率达94.21%。     

模糊PID自整定算法在PLC中的实现

为了将模糊控制理论更好地应用到现场,提出了一种结合MATLAB仿真软件的PLC实现复杂模糊控制算法的快捷方法。实验结果表明,基于S7软件平台实现模糊PID自整定控制算法,对水位控制较常规PID控制调节时间减少90 s,超调量降低4%,改善系统的性能。模糊规则调节过程验证了结合MATLAB的PLC编程灵活性和便捷性。     

聚糖菌反硝化影响因素及内碳源转化特性

在SBR反应器中以乙酸钠为碳源、\mathrm{N}{\mathrm{O}}_3^{-}-N为电子受体成功富集了反硝化聚糖菌，并采用批次实验进一步考察了进水C/N比（3.3,6.7,10）、电子受体（\mathrm{N}{\mathrm{O}}_3^{-}-N、\mathrm{N}{\mathrm{O}}_2^{-}-N）、碳源类型（乙酸钠、葡萄糖）对反硝化聚糖菌活性的影响及内碳源转化特性。实验结果表明，进水C/N比越高，系统\mathrm{N}{\mathrm{O}}_x^{-}-N去除率越高，厌氧段合成PHB越多，但进水C/N比过高会导致普通反硝化菌占优势，影响内碳源反硝化效率，进水C/N比为6.7较为合适；以\mathrm{N}{\mathrm{O}}_3^{-}-N为电子受体长期培养的DGAOs系统未经\mathrm{N}{\mathrm{O}}_2^{-}-N驯化，对\mathrm{N}{\mathrm{O}}_2^{-}-N同样具有良好的反硝化性能，在投加与\mathrm{N}{\mathrm{O}}_3^{-}-N相同浓度的\mathrm{N}{\mathrm{O}}_2^{-}-N后，系统\mathrm{N}{\mathrm{O}}_x^{-}-N去除率达89.6%；当以葡萄糖为碳源时，DPAOs在厌氧段合成的PHB的量仅为以乙酸钠为碳源时合成PHB量的79.5%，且厌氧段葡萄糖利用率仅为72.8%，远远小于乙酸钠的利用率。     

基于遗传算法的箱型结构焊接顺序优化

基于遗传算法原理,建立了箱型结构热-机耦合非线性三维优化仿真模型,以焊接变形为目标函数,进行了焊接顺序数值仿真优化.通过仿真计算优化结果与试验数据比较,证明所提出的优化方法与热-机模型结合是可行的,对于给定的焊接条件,通过选择合适的目标函数,采用遗传算法可以确定最优焊接顺序.这为针对工程具体问题设计焊接工艺提供了可靠的依据.     

Comparative corrosion resistance of plasma-based low-energy nitrogen ion implanted austenitic stainless steel

A high nitrogen face-centered-cubic phase (γ_N) was obtained on the nitrided surface of 1Cr18Ni9Ti austenitic stainless steel by plasma-based low-energy nitrogen ion implantation. No pitting corrosion for the γ_N phase was confirmed by electrochemical polarization measurement in 3% NaCl solution. The protective passive film with a duplex character, iron hydroxide/oxides in the outer region and chromium hydroxide/oxides and iron oxides accompanying chromium and iron nitrides in the inner region, was by 2-3 times thicker than that of original stainless steel. The thick iron hydroxide/oxides region formed on the chromium hydroxide/oxides region due to the increase of alkalinity in the solution, leading to barrier against penetration of localized attack of the aggressive ions. The equivalent general corrosion resistance for the γ_N phase was observed in 0.5 mol/l H₂SO₄ solution relative to the original stainless steel. The passive film formed on the γ_N phase in 0.5 mol/l H₂SO₄ solution was similar to that of original stainless steel. The different role of nitrogen was proposed in pitting corrosion resistance and general corrosion resistance of austenitic stainless steel.     

The eta phases and mechanical properties of TIG welded joints of WC-Co cemented carbide and steel

The tungsten-inert-gas (TIG) arc welding experiments of cemented carbide YG30 and steel 45 were carried out using the Ni-Fe-C filling alloys. The eta phases and mechanical properties of welded joints were analyzed by means of scanning electronic microscope (SEM) , transmission electronic microscope (TEM) coupled with selected diffraction, electronic probe microanalysis and bending strength method. The experimental results show that the chemical composition of the filling alloys affects eta phase formation. When the carbon and nickel contents in filling alloys are O. 61 wt% and 55. 29 wt% ,respectively, no eta phases form. And the joint bending strength is the highest to 1. 352 GPa. But if they are O. 01wt% and 55.38wt%, the eta phases are formed at the boundaries of the cemented carbide and the weld, and the thickness of eta phase layer is about 110 micrometers. And the joint bending strength is low. Usually, these eta phases are anomalously granular,and easy to accumulate at the boundaries between cemented carbides and the weld. They are multiple M6C rich in tungsten and iron.