镁合金大气电偶腐蚀初期规律

研究了AZ91D、AM50、AM60铸造镁合金与A3钢、316L不锈钢、H62黄铜、LY12铝合金组成的电偶对分别在青岛和武汉现场暴晒3个月和6个月后的大气电偶腐蚀行为及规律.结果显示, 镁合金始终是电偶对的阳极; 当其与其它4种材料偶接时, 其腐蚀速率增加.镁合金与A3钢偶合后, 其大气电偶腐蚀效应最大, 而与LY12铝合金组成的电偶对的大气电偶腐蚀效应最小.不同镁合金的大气电偶腐蚀效应存在如下关系: γAZ91D>γAM50>γAM60.暴晒3个月后, 青岛的大气电偶腐蚀效应明显高于武汉的大气电偶腐蚀效应.随着暴晒时间的延长, 青岛和武汉的大气电偶腐蚀效应分别呈降低和升高的趋势.     

镁合金在大气环境中电偶腐蚀行为及规律的研究

在北京大气环境下，研究AM60镁合金和不同金属材料（碳钢、不锈钢、黄铜和铝合金）偶接的电偶腐蚀行为规律。研究表明，镁合金作为阳极发生不同程度的电偶腐蚀，通过1a的北京大气环境下的暴露试验后，AM60镁合金的电偶腐蚀效应由强到弱的顺序为：碳钢、黄铜、不锈钢和铝合金，其中镁合金与LY12铝合金偶接的电偶腐蚀效应最小。通过与其它地区室外暴晒的镁合金电偶腐蚀效应的对比，表明环境因素影响着镁合金的电偶腐蚀效应。同时阴极材料、试验时间、试样尺寸（偶接面积）和试验环境都会对镁合金电偶腐蚀效应产生影响。经1a曝晒的AM60镁合金形成了具有保护性的腐蚀产物层阻碍了腐蚀发展。北京地区高自然降尘量导致金属表面湿润时间加大，从而加速了AM60镁合金的电偶腐蚀。采用XRD方法分析表面的腐蚀产物，用金相显微镜和扫描电镜（SEM）观察试样腐蚀后的表面形貌特征和腐蚀产物的结构，并用与之相连的能谱仪分析腐蚀产物中的元素组成。     

镁合金在大气环境中电偶腐蚀行为及规律的研究

研究了北京大气环境下，AM50镁合金作为阳极发生不同程度的电偶腐蚀行为规律。结果表明其中镁合金与LY12铝合金偶接的电偶腐蚀效应最小。通过与其他地区室外暴晒的镁合金电偶腐蚀效应对比，表明环境因素，尤其是试验开始初期阶段的大气环境状况对于镁合金初期电偶腐蚀行为有着重要的影响。同时阴极材料、试验时间、试样尺寸（偶接面积）和试验环境都会对镁合金电偶腐蚀效应产生影响。采用XRD分析表面的腐蚀产物，用金相显微镜和扫描电镜（SEM）观察试样腐蚀后的表面形貌特征和腐蚀产物的结构，并用与之相连的能谱仪分析腐蚀产物中的元素组成。     

微等离子体氧化陶瓷膜对钛合金接触腐蚀的影响

在铝酸钠溶液中，利用微等离子体氧化技术，在TC4钛合金表面原位生长复合氧化物陶瓷膜，研究了陶瓷膜的相组成、形貌和陶瓷膜对钛合金接触腐蚀的影响。陶瓷膜由Al2TiO5，α-Al2O3和RutileTiO2构成；整个膜层由致密层和疏松层组成。陶瓷膜层改善了钛合金与LY12铝合金和H62黄铜的接触腐蚀，陶瓷膜层使得钛合金与LY12铝合金电偶对的电偶电流降低为原来的1／7，使得钛合金与H62黄铜的电偶电流降低为原来的1／2。     

微等离子体氧化陶瓷膜对钛合金接触腐蚀的影响

在铝酸钠溶液中,利用微等离子体氧化技术,在TC4钛合金表面原位生长复合氧化物陶瓷膜,研究了陶瓷膜的相组成、形貌和陶瓷膜对钛合金接触腐蚀的影响.陶瓷膜由Al2TiO5,α-Al2O3和Rutile TiO2构成;整个膜层由致密层和疏松层组成.陶瓷膜层改善了钛合金与LY12铝合金和H62黄铜的接触腐蚀,陶瓷膜层使得钛合金与LY12铝合金电偶对的电偶电流降低为原来的1/7,使得钛合金与H62黄铜的电偶电流降低为原来的1/2.     

基于电偶的大气腐蚀性检测仪的研制及应用

针对大气腐蚀研制了基于电偶的大气腐蚀性检测仪,其对电偶电流进行模拟积分，输出电偶电量值，用来研究金属材料的大气腐蚀性.并用于不同氯离子浓度薄液膜下LY12铝合金大气腐蚀性检测，结果表明该仪器具有较好的性能，可用于现场测试和监测.     

碳纤维复合材料与LY12铝合金的电偶腐蚀

依据相关标准研究了碳纤维复合材料与LY12铝合金的电偶腐蚀行为,结果表明,碳纤维与LY12铝合金在NaCl溶液中接触时会发生较为严重的电偶腐蚀,环境温度、电解液浓度和pH对电偶电流有较大的影响。电偶电流随偶接时间的增加大体上呈下降的趋势,当电解液体系在酸性或碱性条件下,电偶电流先增大后降低,并保持在一个较高的水平;而在中性条件下电偶腐蚀电流相对最小。LY12铝合金电偶腐蚀后,表面有明显的点蚀坑,且腐蚀区域变得较为平整。     

镁、铝合金间的连接腐蚀行为及不同表面处理的保护效果研究

按照GB/T10125-1997《人造气氛腐蚀试验盐雾试验》试验标准,采用对比试验,对镁合金与铝合金连接的腐蚀行为进行研究。结果表明:由于镁合金电极电位低于铝合金,因此,镁合金与铝合金连接后,置于含NaCl的腐蚀气氛时,发生电偶腐蚀,加速了镁合金的全面腐蚀;当对镁合金进行适当的表面处理后,腐蚀明显减少,且有电偶腐蚀效应大大减小;在两种表面处理工艺的对比中,微弧氧化处理效果较佳。     

模拟大气环境中加速镁合金电偶腐蚀的研究

研究了压铸镁合金AZ91D分别与黄铜、铝合金、316L不锈钢和A3钢组成的电偶在模拟的大气环境即盐雾和湿热的加速腐蚀试验中的电偶腐蚀行为及规律.结果表明:在此气相环境中，镁合金腐蚀倾向显著;多种因素可以加速镁合金的电偶腐蚀；盐雾实验中，盐的浓度、大阴极小阳极的面积比以及阴极材料相对于镁阳极的尺寸是加速镁合金电偶腐蚀的重要因素.      

碳纤维复合材料与铝合金电偶腐蚀行为研究

采用全浸腐蚀、腐蚀失重测量、电偶电位和电偶腐蚀电流等试验研究方法．将T300／5222、T300／5405和T300／QY8911三种碳纤维复合材料与LY12CZ、71304和2D70三种铝合金相互偶接，研究由于电偶腐蚀的存在，对铝合金及复合材料腐蚀行为的影响，用SEM方法观察其腐蚀形貌．结果表明，碳纤维复合材料与铝合金的电偶腐蚀作用，促进了铝合金表面点蚀的形成与扩展，电偶作用使铝合金腐蚀的溶解速率明显加快，而与铝合金偶接的复合材料表面形貌基本无变化，复合材料与铝合金之间电偶腐蚀电流较大，二者之间电偶腐蚀十分严重．     

Effect of passive film on the galvanic corrosion of titanium alloy Ti60 coupled to copper alloy H62

Ti alloys exhibit high potential because of the compact passive film. However, the effect of passive film on galvanic corrosion is not clear. On the one hand, the great potential difference can accelerate the galvanic corrosion of other metals with low potential. On the other hand, the passive film can hinder the electrochemical reactions, inhibiting the galvanic corrosion. To clarify this question, the galvanic corrosion of titanium alloy Ti60 coupled to copper alloy H62 was studied using zero‐resistance ammeter, scanning vibrating electrode technique, scanning electron microscopy, and potentiodynamic polarization measurements. The chemical composition and electrical properties of the passive film on Ti60 were detected using X‐ray photoelectron spectroscopy and Mott‐Schottky plots. The results indicate the galvanic corrosion of Ti60‐H62 coupling is ignorable in spite of the great galvanic potential difference between them. It can be attributed to the low electron donor density of passive film, which inhibits the electron charge transfer process at the film/solution interface, causing the slow cathodic reaction rate on Ti60.     

Comparison of corrosion behaviors of AZ31, AZ91, AM60 and ZK60 magnesium alloys

The corrosion behaviours of four kinds of rolled magnesium alloys of AZ31, AZ91, AM60 and ZK60 were studied in 1 mol/L sodium chloride solution. The results of EIS and potentiodynamic polarization show that the corrosion resistance of the four materials is ranked as ZK60＞AM60＞AZ31＞AZ91. The corrosion processes of the four magnesium alloys were also analyzed by SEM and energy dispersive spectroscopy(EDS). The results show that the corrosion patterns of the four alloys are localized corrosion and the galvanic couples formed by the second phase particles and the matrix are the main source of the localized corrosion of magnesium alloys. The corrosion resistance of the different magnesium alloys has direct relationship with the concentration of alloying elements and microstructure of magnesium alloys. The ratio of the β phase in AZ91 is higher than that in AZ31 and the β phase can form micro-galvanic cell with the alloy matrix, as a result, the corrosion resistance of AZ31 will be higher than AZ91. The manganese element in AM60 magnesium alloy can form the second phase particle of AlMnFe, which can reduce the Fe content in magnesium alloy matrix, purifying the microstructure of alloy, as a result, the corrosion resistance of AM60 is improved. However, due to the more noble galvanic couples of AlMnFe and matrix, the microscopic corrosion morphology of AM60 is more localized. The zirconium element in ZK60 magnesium alloy can refine grain, form stable compounds with Fe and Si, and purify the composition of alloy, which results in the good corrosion resistance of ZK60 magnesium alloy.     

Corrosion of magnesium alloys in commercial engine coolants

A number of magnesium alloys show promise as engine block materials. However, a critical issue for the automotive industry is corrosion of the engine block by the coolant and this could limit the use of magnesium engine blocks. This work assesses the corrosion performance of conventional magnesium alloy AZ91D and a recently developed engine block magnesium alloy AM‐SC1 in several commercial coolants. Immersion testing, hydrogen evolution measurement, galvanic current monitoring and the standard ASTM D1384 test were employed to reveal the corrosion performance of the magnesium alloys subjected to the coolants. The results show that the tested commercial coolants are corrosive to the magnesium alloys in terms of general and galvanic corrosion. The two magnesium alloys exhibited slightly different corrosion resistance to the coolants with AZ91D being more corrosion resistant than AM‐SC1. The corrosivity varied from coolant to coolant. Generally speaking, an organic‐acid based long life coolant was less corrosive to the magnesium alloys than a traditional coolant. Among the studied commercial coolants, Toyota long life coolant appeared to be the most promising one. In addition, it was found that potassium fluoride effectively inhibited corrosion of the magnesium alloys in the studied commercial coolants. Both general and galvanic corrosion rates were significantly decreased by addition of KF, and there were no evident side effects on the other engine block materials, such as copper, solder, brass, steel and aluminium alloys, in terms of their corrosion performance. The ASTM D 1384 test further confirmed these results and suggested that Toyota long life coolant with 1%wt KF addition is a promising coolant for magnesium engine blocks.     

Galvanic corrosion of aluminium alloy members of bridge guiderails under severe atmospheric exposure conditions

ABSTRACT

Aluminium alloys are nowadays preferred as materials for bridge guiderails especially for bridges connecting oceanic islands or spanning inlets due to their inherent corrosion resistance. But because of the limited mechanical strength of aluminium alloy, fasteners of guiderail members are made from steel materials. It has been found that contact between bare steel fasteners and aluminium alloy members can cause galvanic corrosion in the aluminium alloy. Research was carried out to investigate the capability of different surface treatments on fasteners and aluminium alloy members to inhibit galvanic corrosion under atmospheric exposure for periods of one and three years. It was found, among other results, that stainless steel fasteners treated with zinc flake coating were the most effective inhibitors of galvanic corrosion on aluminium alloy members.     

GALVANIC CORROSION AND PROTECTION OF GECM／LY12CZ COUPLES UNDER DIFFERENT ATMOSPHERIC EXPOSURE CONDITIONS

Galvanic, compatibility between graphite epoxy composite materials (GECM) and LY12CZ aluminum alloy was evaluated in different atmospheric corrosion environments and by laboratory electrochemical measurements. Open circuit potential electrochemical measurements showed a relatively large potential difference about 1 volt between the GECM and LY12CZ aluminum alloy, and this difference provided the driving force for galvanic corrosion of the LY12CZ aluminum alloy as an anode. Having been exposed for 1, 3 or 5 years in Beijing, Tuandao and Wanning station, GECM/LY12CZ couples showed significant losses of strength and elongation. Protective coatings and non-conductive barriers breaking the galvanic corrosion circuit were evaluated under the same atmospheric corrosive conditions. Epoxy primer paint, glass cloth barriers and LY12CZ anodizing were effective in galvanic corrosion control for GECM/LY12CZ couples.     

铝合金在海洋环境中的腐蚀研究(Ⅱ)--海水全浸区16年暴露试验总结

总结了铝合金在青岛海域海水全浸区暴露16年的腐蚀结果，防锈铝LF2Y2，LF6M（BL），F21M，180YS在海水全浸区有好的耐蚀性，工业纯铝L4M，锻铝LD2CS的耐蚀性较差，无包铝层的硬铝LY12CZ和超硬铝LC4CS在海水中的耐蚀性很差，硬铝，超硬铝的包铝层起牺牲阳极作用，使基体受到保护，海生物污损对铝合金在海水中的腐蚀有明显影响，镁、锰能提高铝的耐海水腐蚀性，硅明显降低铝的耐蚀性，铜严重损害铝的耐蚀性，腐蚀电位较负的铝合金耐海水腐蚀性较好，腐蚀电位较正的铝合金耐海水腐蚀性较差。