铜镍合金海水腐蚀的表面与界面特征研究

采用金相（ＯＭ）、俄歇（ＡＥＳ）、扫描电镜（ＳＥＭ）及透射电镜（ＴＥＭ）等技 术手段对实海暴露试样进行探测分析,揭示了表面膜缺陷（如碳膜）、晶界缺陷（晶界析出物）等加速该 合金腐蚀进程的试验现象和内在根据,特别指出影响该合金海水腐蚀产物膜稳定性的主要因素,分析了其中的沿晶扩散及应变诱生调峰分解与沿晶腐蚀、沿晶脆断的相互关系。     

AI—Mg合金在不同pH值的NaCI溶液中的腐蚀行为

用电化学阻抗谱（ＥＩＳ）技术研究了ＬＦ３Ｍ和ＬＦ１１Ｍ两种Ａ１－Ｍｇ合金在不同ｐＨ值的２．７％ＮａＣＩ溶液中的腐蚀行为。结果表明，Ａ１－Ｍｇ合金在不同ｐＨ值的ＮａＣＩ溶液中不同极化电位下处于不同的腐蚀状态，阻抗谱呈现不同的特征，分析了Ａ１－Ｍｇ合金在厦门海域显示较强的局部腐蚀敏感性的原因。     

新型铸造合金的组织及其腐蚀行为的AFM研究

对新设计新型铸造合金有用金相显微镜，Ｘ射线衍射，电子探针（ＥＭＰＡ）、扫描电镜（ＳＥＭ）及原子力显微镜（ＡＦＭ）研究了合金的组织及其腐蚀行为，试验结果表明，该合金经１１５０℃固溶处理后，具有良好的耐蚀性能。通过ＡＦＭ的观测，得到了新型铸造合金的超高分辨的三维腐蚀形貌图象，为该合金的开发应用奠定了技术基础。     

8090Al－Li合金冲击断裂行为的SEM研究

８０９０Ａｌ－Ｌｉ合金冲击断裂行为的ＳＥＭ研究王轶农，张淑芹，李星逸，孟祥才，廖波（佳木斯工学院）（燕山大学）１前言Ａｌ－Ｌｉ合金与常规Ａｌ合金相比，具有低密度、高比强度和高比刚度等优点，是一种新型航空航天结构材料。但该合金时效态具有较高的沿晶断裂倾...     

新型高硅铸造镍钼合金的组织及腐蚀行为的研究

设计了新型高硅铸造镍钼合金的化学成分,采用金相显微镜、ｘ射线衍射、电子探针（ＥＭＰＡ）、透射电镜（ＴＥＭ）、扫描电镜（ＳＥＭ）及扫描隧道显微镜（ＳＴＭ）研究了该合金的组织及其腐蚀行为。试验结果表明,新型高硅铸造镍钼合金经１２２０℃固溶处理后,可得到单一的奥氏体组织,具有良好的耐蚀性能。并通过ＳＴＭ的观测,得到了新型合金的超高分辨的三维腐蚀形象图象,为该合金的开发应用奠定了技术基础。     

QAl-9-2合金在3.5%NaCl溶液中脱合金腐蚀研究

利用扫描隧道显微镜（ＳＴＭ）对ＱＡｌ－９－２合金在３．５％ＮａＣｌ溶液中脱合金腐蚀的早期过程进行了原位观察,结合ＳＥＭ,ＥＤＸ分析ＱＡｌ－９－２合金的脱合金腐蚀首先发生在α基体和亚稳β相的界面,并在亚稳β相内的继续扩展,α相不发生脱合金腐蚀,ＳＴＭ原位观察没有发现铜在表面再沉积的现象。     

N－105合金在NaNO_3和Na_2O_2沉积盐层中的高温氧化行为

用Ｘ－射线衍射、ＳＥＭ及ＥＤＡＸ方法研究了Ｎ－１０５合金在７００℃，ＮａＣＯ３和Ｎａ２Ｏ２沉积盐层中的高温氧化行为．结果表明，合金在ＮａＮＯ３沉积盐层中的腐蚀比Ｎａ２Ｏ２沉积盐层中更为严重．     

铝及铝合金在熔融钠中的腐蚀行为

研究了纯铝，Ａｌ－Ｓｉ和Ａｌ－Ｍｇ合金在３５０～４５０℃熔融钠中的腐蚀行为，采用ＯＭ，ＸＲＤ，ＥＤＡＸ和ＥＰＭＡ分析了腐蚀产物的组织形貌和合金元素的分布，实验结果表明高纯铝受到轻微的腐蚀，并非完全“免蚀”，工业纯铝的腐蚀较明显，主要发生在杂质偏聚的晶界附近，铝合金的腐蚀程度取决于杂质元素尤其是硅的含量，铝中添加一定量的镁并用向量锆细化晶粒可改善合金对熔融钠的耐蚀性，铝和铝合金的腐蚀产物经测定的Ａｌ     

DZ—22合金和VPS MCrAlY涂层材料高温腐蚀试验研究

采用表面涂盐法进行了ＤＺ－２２合金和真空等离子喷涂（ＶＰＳ）的几种ＭＣｒＡｌＹ涂层材料在９００℃空气中的腐蚀性能试验。结果表明，热盐的存在加速了ＤＺ－２２合金的腐蚀，ＶＰＳ的ＭＣｒＡｌＹ涂层材料热腐蚀试验时在其表面生成一层致密的α－Ａｌ２Ｏ３薄膜，因而具有优异的耐高温腐蚀性能。     

内氧化粉体制备的Ag-SnO2接点材料的显微结构

Ａｇ－Ｓｎ－Ｍ（Ｍ＝Ｂｉ、Ｃｕ）合金粉末内氧化后经压制、烧结、挤压、加工制备成Ａｇ－ＳｎＯ２接点材料,用光学显微镜,Ｘ射线衍射和ＳＥＭ研究其显微结构,结果表明：在Ａｇ－ＳｎＯ２材料中存在Ａｇ,ＳｎＯ２、Ｂｉ２ＳｎＯ７和ＣｕＯ,氧化物以极细小的颗粒分布在银基体中。     

Al含量和烧结温度对Ti_(50)Ni_(50)与Ti_(47)Ni_(47)Al_6合金耐蚀性的影响

采用粉末冶金方法制备了Ti_(50)Ni_(50)与Ti_(47)Ni_(47)Al_6合金,通过极化曲线、配备能谱分析的扫描电镜测试手段研究了Al含量和烧结温度对烧结合金耐蚀性的影响。结果表明:1080℃烧结Ti_(50)Ni_(50)合金表现为钝化特征,蚀孔尺寸较小,弥散分布;Al含量为6%时,合金表现为活性溶解,蚀孔尺寸及腐蚀区域面积显著增加,耐蚀性降低;烧结温度提高至1180℃时,合金重新表现为钝化,蚀孔尺寸及腐蚀区域面积显著减小,耐蚀性最佳。     

AISI 316不锈钢和Ti6Al4V合金在海水环境中的腐蚀与腐蚀磨损行为(英文)

采用立式万能销盘腐蚀磨损试验机研究AISI 316不锈钢和Ti6Al4V合金在海水中与Al2O3陶瓷对磨时的腐蚀与腐蚀磨损行为,重点讨论腐蚀磨损之间的交互作用。结果表明,摩擦作用使得Ti6Al4V合金和316不锈钢的开路电位大幅下降,腐蚀磨损过程中的电流密度远高于静态腐蚀时的电流密度,摩擦明显促进了合金的腐蚀。两种合金在海水中的磨损量远大于在纯水中的磨损量,腐蚀促进了磨损,并且Ti6Al4V合金的耐磨性优于316不锈钢的耐磨性,腐蚀磨损之间的交互作用是材料损失的一个重要因素。本实验所用的摩擦装置为单向滑动的面面接触方式,这使得摩擦对腐蚀的促进作用在总磨损量中所占的比例很小。     

Review of micro-scale and atomic-scale corrosion mechanisms of second phases in aluminum alloys

Localized corrosion of aluminum (Al) alloys, such as pitting corrosion, intergranular corrosion, and stress corrosion cracking is closely related to the micro-galvanic corrosion between the second phase and the Al matrix. Using high-resolution transmission electron microscopy and first principles calculations, the factors that affect corrosion mechanisms of the second phase in Al alloys at micro-scale and atomic-scale were examined, including the composition and structure of second phase, pH of the environment, stress and adsorption behavior of adsorbates (such as Cl⁻, H₂O, OH⁻ and O²⁻).     

Al对低中子吸收截面Ti-Zr-Nb高熵合金的微观结构和腐蚀行为的影响

针对Al对低中子吸收截面Ti-Zr-Nb系高熵合金的微观结构和腐蚀行为进行了研究。比较了不含Al和含15at%Al的Ti-Zr-Nb合金的相图、微观结构、氧化行为和腐蚀行为。相图计算结果表明,在熔点下Ti-Zr-Nb三元合金为bcc相,添加的Al会倾向于在合金中形成不同的金属间化合物,而缩小相图中bcc单相区的温度区。XRD和TEM结果表明,熔炼获得的Ti-Zr-Nb三元合金为简单的bcc结构,而Al会导致晶体结构转变为有序的B2结构。通过热重分析和高压釜试验对Ti-Zr-Nb系高熵合金的腐蚀行为进行了研究。结果表明,在腐蚀过程中,Ti-Zr-Nb三元合金的氧化膜容易发生剥落,而添加Al会提高氧化层的稳定性,但不会改变腐蚀氧化层的主要氧化物种类。通过计算反应速率常数和激活能对氧化动力学进行了研究,发现添加Al的Ti-Zr-Nb系合金的高温氧化性能与Zr合金接近。     

稀土Ce对Pb-Mg-Al屏蔽材料组织和耐蚀性的影响

采用腐蚀失重试验和动电位极化曲线扫描测试手段,研究Ce元素对Pb-Mg-Al合金在3.5%（质量）NaCl溶液中腐蚀性能的影响。研究结果表明：随着Ce含量的增加,稀土Ce与合金中的Al形成弥散、均匀的金属间化合物Al4Ce,进一步提高了合金的耐蚀性。     

Microstructures and corrosion behaviors of Al–6.5Si–0.45Mg–xSc casting alloy

The microstructures and corrosion behaviors of the Al–6.5Si–0.45Mg casting alloys with the addition of Sc were investigated by using scanning electron microscopy, X-ray diffraction, electrochemical measurement techniques and immersion corrosion tests and compared with those of Sr-modified alloy. The results show that Sc has evident refining and modifying effects on the primary α(Al) and the eutectic Si phase of the alloy, and the effects can be enhanced with the increase of Sc content. When the Sc content is increased to 0.58 wt.%, its modifying effect on the eutectic Si is almost same as that of Sr. Sc can improve the corrosion resistance of the test alloy in NaCl solution when compared with Sr, but the excessively high Sc content cannot further increase the corrosion resistance of the alloy. The corrosion of the alloys mainly occurs in the eutectic region of the alloy, and mostly the eutectic α(Al) is dissolved. This confirms that Si phase is more noble than α(Al) phase, and the galvanic couplings can be formed between the eutectic Si and α(Al) phases.     

Localized corrosion mechanism associated with precipitates containing Mg in Al alloys

To clarify the localized corrosion mechanism associated with precipitates containing Mg in Al alloys, the simulated bulk precipitates of S and β were synthesized through melting and casting. Their electrochemical behaviors and coupling behaviors with α（Al） in NaCl solution were measured. Meanwhile, simulated Al alloys containing S and β particles were prepared and their corrosion morphologies were observed. It＇s found that there exist two kinds of corrosion mechanisms associated with precipitates containing Mg. The precipitate of β is anodic to the alloy base, resulting in its anodic dissolution and corrosion during the whole corrosion process. While, there exists a corrosion conversion mechanism associated with the S precipitate, which contains active element Mg and noble element Cu simultaneously. At an initial stage, S is anodic to the alloy matrix at its periphery and the corrosion occurs on its surface. However, during its corrosion process, Mg is preferentially dissolved and noble Cu is enriched in the remnants. This makes S become cathodic to a（Al） and leads to anodic dissolution and corrosion on the alloy base at its periphery at a later stage.     

Effect of N-ion implantation and diamond-like carbon coating on fretting wear behaviors of Ti6Al7Nb in artificial saliva

The tribology behaviors of Ti6Al7Nb, its alloy with N-ion implantation, and its alloy with diamond-like carbon (DLC) coating were investigated in artificial saliva. Fretting wear tests of untreated, N-ion implanted and DLC coated Ti6Al7Nb alloys plate against a Si₃N₄ ball were carried out on a reciprocating sliding fretting wear test rig. Based on the analysis of X-ray diffraction, Raman spectroscopy, 3-D profiler, SEM morphologies and frictional kinetics behavior analysis, the damage behavior of surface modification layer was discussed in detail. The results indicated that the fretting wear behavior of Ti6Al7Nb alloy with N-ion implantation was increased with the dose increase of the implanted nitrogen ions. Moreover, the DLC-coated Ti6Al7Nb alloy with low ion implantation could improve the fretting wear behavior greatly. In addition, the Ti6Al7Nb with DLC coating had better corrosion resistance due to the special compact structure. All results suggested that the Ti6Al7Nb with DLC coating had better wear resistance than that with N-ion implantation in artificial saliva.     

冷热循环对颗粒增强铝基复合材料微屈服行为的影响

采用微屈服强度测试、透射电镜和高分辨透射电镜分析,对经过不同冷热循环工艺处理后的颗粒增强铝基复合材料的微屈服行为进行了研究。结果表明,冷热循环次数虽然对颗粒增强铝基复合材料微屈服行为的宏观规律没有本质的影响,但是仍然影响颗粒增强铝基复合材料的微屈服行为。对球形颗粒而言,小应变量下的微屈服强度随冷热循环次数的增加而增高;但对棱形颗粒而言,循环次数的影响较为复杂。研究还表明,冷热循环次数影响颗粒增强铝基复合材料微屈服行为的主要原因是其位错组态和残余应力在不同的循环次数下有明显的不同。     

Simulation on function mechanism of T1(Al2CuLi) precipitate in localized corrosion of Al-Cu-Li alloys

To clarify the corrosion mechanism associated with the precipitate of Tl(Al₂CuLi) in Al-Li alloys, the simulated bulk precipitate of T1 was fabricated through melting and casting. Its electrochemical behavior and coupling behavior with (Al) in 3.5% NaCl solution were investigated. Meanwhile, the simulated Al alloy containing T1 particle was prepared and its corrosion morphology was observed. The results show that there exists a dynamic conversion corrosion mechanism associated with the precipitate of T1. At the beginning, the precipitate of T1 is anodic to the alloy base and corrosion occurs on its surface. However, during its corrosion process, its potential moves to a positive direction with immersion time increasing, due to the preferential dissolution of Li and the enrichment of Cu. As a result, the corroded T1 becomes cathodic to the alloy base at a later stage, leading to the anodic dissolution and corrosion of the alloy base at its adjacent periphery. It is suggested that the localized corrosion associated with the precipitate of T1 in Al-Li alloys is caused by the alternate anodic dissolution of the T1 precipitate and the alloy base at its adjacent periphery.