几种铝合金切屑的热挤压再利用

将AA6060,AA6082和AA7075铝合金生产中的切屑压或坯料,热挤出矩形轮廓,最后轮廓特性直接转化为技术的工艺过程链。这表明．利用直接转化技术。就不必进行切屠二次熔炼了。直接转化技术能通过减少工艺过程链的长度和减少能量需求来降低生产成本。挤压过程显示了一些切属是不同种类合金切屑的混合压制和固接。通过合金的混合压制,制件的力学性能能够大大提高。     

切削速度对切屑形态和加工表面微观形貌的影响

为了研究钛合金车削过程中切削速度和切屑形态特征对已加工表面微观形貌的影响。采用硬质合金涂层刀具车削钛合金TC4,研究了切削速度对切屑形态特征、已加工表面粗糙度和轮廓最大高度的影响规律,分析了切屑底部毛边形貌、已加工表面形貌与表面粗糙度三者之间的关系。结果表明:在切削速度40~120m/min时,切屑底边出现锯齿形毛边,且随切削速度增大锯齿越明显。切屑底部锯齿毛边的形成是造成已加工表面波峰损伤形成的主要原因。影响已加工表面粗糙度的微观形貌特征包括硬质颗粒、粘结现象和波峰损伤。因此,为了获得高质量的加工表面,加工参数选择时必须规避硬质颗粒和严重的粘结现象,并控制切屑底部毛边形态特征。     

衬板轧制铝/镁/铝复合板的波纹界面结构及形成机理（英文）

提出一种采用衬板轧制进行AA1060铝/AZ31B镁/AA1060铝复合板的制备方法。结果表明：传统轧制铝/镁/铝复合板截面轮廓较为平直，而衬板轧制由于衬板可将剪切力部分转化为压应力，从而改变复合板板受力状态，在铝/镁界面连接处形成差速流动，故而界面轮廓呈现波浪状特征，层间实现互锁连接。界面连接强度为64 MPa，是传统轧制复合板的4倍。力学性能测试表明：衬板轧制复合板的抗拉强度可达210 MPa，比传统轧制法提高12.3%。综上可知，衬板轧制法为高性能铝/镁/铝异质复合板成形制造提供一种新思路。     

近年来关于硬质合金刀片切屑控制研究的新成果

在当代技术背景下，对切屑控制问题进行深入的研究，具有重要的意义。研究的内容包括三个方面，即切屑的生成学、切居卷曲以及切屑的折断力学。本文主要阐述近年来关于硬质合金刀片切屑流向、切屑卷曲以及切清折断研究的一些新成果．     

铸铁切屑熔炉的设计及应用

分析了铸铁切屑熔炼的特点，提出了铸铁切屑熔炉设计的原则，设计出一种适合铸铁切屑熔炼的冶金冲天炉，能够将铸铁切屑熔炼成灰口铸铁，操作简单，回收率高。     

切削速度对锯齿形切屑形成的影响规律

为研究TC4切削加工过程中切削速度对锯齿形切屑破坏程度的影响,对TC4进行单因素切削试验，分析TC4的动态行为，并进行有限元仿真，进一步探究锯齿形切屑影响因素以及切屑与切削速度之间的联系。结果表明：在TC4切削过程中，随着切削速度的提高，切屑的锯齿状越来越明显；通过数值计算得出，TC4的能量势垒随着切削速度增大而降低，而绝热剪切带内部应力、应变随着切削速度提高而增大，切削速度越高越容易形成锯齿形切屑。     

铁屑压块冷风化铁炉熔炼铸铁和生铁

铁屑压块冷风化铁炉熔炼铸铁和生铁王富宽（威海电视大学山东威海市：２６４２００）主题词：切屑，冲天炉钢铁切屑是利用价值很高的资源。生铁价格上涨居高不下，切屑的利用更显必要。目前，利用切屑的主要途径是直接入炉炼制再生生铁。再生铁含硫较高，一般在０．０８％...     

NC车削加工切屑形成机理的有限元仿真

有限元分析已经被广泛的应用于金属切削加工过程中切屑形成的建模与仿真。根据切屑的几何参数，给出了不同类型切屑的三维实体模型；介绍了三维卷曲切屑的有限元建模的方法和切屑折断的条件；并对其中的一例模型进行了有限元建模和分析，将有限元仿真结果和实验分析结果进行了比较，具有很好的一致性。证实了有限元仿真对切屑形成的预测能力。最后。提出切屑形成机理和有限元发展中存在的问题以及未来的研究方向。     

AZ80镁合金切屑回用的探讨

试验材料主要采集于车床上加工切削AZ80镁合金时所产生的切屑，主要化学成分见表1。要求切屑干净，最好是不带油污或其他切屑等有害杂质。     

钛合金高速切削切屑形成机理的有限元分析

钛合金在切削加工时容易产生锯齿状切屑，周期性的锯齿状切屑会引起切削力高频波动，从而影响加工表面质量和刀具寿命。然而其切屑形成的机理尚无统一的结论。本研究采用刚塑性有限元模型以及正交化Cockroft—Latham断裂准则，对钛合金Ti6A14V高速正交切削进行了仿真。仿真结果显示，周期性断裂理论能很好地解释钛合金锯齿状切屑形成的机理，主剪切变形区应力状态的变化是裂纹萌生与扩展的主要原因。研究结论与相关试验切屑显微照片特征相吻合，可以为实现钛合金高速切削提供理论依据和技术支持。     

Degradation of the corrosion resistance of anodic oxide films through immersion in the anodising electrolyte

The deterioration of AA2024, AA6061 and AA7475 anodised in an environmentally-compliant tartaric acid/sulphuric acid electrolyte has been examined as a function of the immersion time in the electrolyte after termination of anodising. By transmission electron microscopy and scanning electron microscopy, degradation of the porous oxide film was qualitatively observed on AA2024. Electrochemical impedance spectroscopy revealed that AA2024 and AA7075 were more sensitive to prolonged immersion in the anodising electrolyte compared with AA6061, due to increased barrier layer thinning rates and increased susceptibility to localized corrosion. Salt spray tests confirmed the previous, indicating decay of anticorrosion performance for AA2024 and AA7075.     

The influence of burr formation and feed rate on the fatigue life of drilled titanium and aluminium alloys used in aircraft manufacture

Following drilling, fatigue life trials were performed on as-drilled and deburred specimens made from Ti–6Al–4V, AA7010 and AA2024, with feed rates varied at 2 levels. Deburring dramatically increased the fatigue performance of the Ti–6Al–4V and AA7010 samples by 69% and 283% respectively, but there was no significant effect on the AA2024 alloy. Fractography showed failure initiated near the exit burrs in Ti–6Al–4V and AA7010 specimens but not in the AA2024 workpieces. Correlation (R²) of fatigue notch factor against the sum of entrance and exit burr height was 0.68 and 0.79 for Ti–6Al–4V and AA7010 respectively, compared to 0.54 for AA2024.     

Galvanic compatibility of corrosion protective coatings with AA7075 aluminum alloy

The galvanic compatibility of aerospace aluminum alloy AA7075 with cadmium (Cd), zinc (Zn), and zinc–cobalt–iron (Zn–Co–Fe, 32–37%Co and 1%Fe) alloys was investigated. A comparison of open circuit potential [OCP vs. saturated calomel electrode (SCE)] measurements in 0.6 mM NaCl showed that all coatings would act anodically to AA7075 with an exception of Zn–Co–Fe (37%Co + 1%Fe) alloy which was electropositive to AA7075. During the zero resistance ammetry (ZRA) measurement in 0.6 M NaCl electrolyte the coupled OCP and current density were measured during 7 days of immersion and both Zn and Cd acted anodic and thus sacrificial to AA7075. Galvanic coupling of AA7075 with (37%Co + 1%Fe) Zn–Co–Fe alloy resulted in the consequent dissolution of the AA7075 aluminum alloy. In contrast, Zn–Co–Fe (32%Co + 1%Fe) alloy was found to be anodic to AA7075 during the first 26 h of immersion but after dezincification and cobalt enrichment at the surface became cathodic to the AA7075 aluminum alloy. During coupling with Zn, some pitting was also observed on AA7075.     

Formability of AA5052/polyethylene/AA5052 sandwich sheets

The formability of AA5052/polyethylene/AA5052 sandwich sheets was experimentally studied. Three kinds of AA5052/polyethylene/AA5052 sandwich specimens with different thicknesses of core materials were prepared by the hot pressing adhesive method. Then, the uniaxial tensile tests were conducted to investigate the mechanical properties of AA5052/polyethylene/ AA5052 sandwich sheets, and the stretching tests were carried out to investigate the influences of polymer core thickness on the limit dome height of the sandwich sheet. The forming limit curves for three kinds of sandwich sheets were obtained. The experimental results show that the forming limit of the AA5052/polyethylene/AA5052 sandwich sheet is higher than that of the monolithic AA5052 sheet, and it increases with increasing the thickness of polyethylene core.     

Microstructure and mechanical properties of friction stir welded aluminium alloys with special reference to AA 5083 and AA 6082

Abstract

Aluminium alloys AA 5083 and AA 6082 have been friction stir welded and the mechanical properties and microstructures of the welds have been evaluated. Alloy AA 5083 mainly fractured near the centre of the weld, while fracture in AA 6082 mainly occurred in the heat affected zone. The tensile strength of welded joints in AA 6082 was lower than the base material strength, but still met classification societies' requirements. Hardness was approximately constant across the welded zone in AA 5083, while a minimum in hardness was found in the AA 6082 welds. The location of the fracture closely matched the minimum hardness region. Very fine scale precipitation in AA 6082 was significantly affected by the weld thermal cycle. In the zone of lowest hardness, the hardening precipitate (β″-Mg₅Si₆) had transformed to the non-hardening β′-Mg_1.7Si. This is probably the main reason for the minimum in hardness, the fracture location, and the decreased tensile strength. Results are compared to a similar investigation of aluminium alloy AA 7075.     

Corrosion pathways in aluminium alloys

The corrosion pathways in AA2024-T3, AA5083-O and AA6082-T6 alloys have been investigated. The objective of the investigation is to further the understanding of the complex localised corrosion mechanism in aluminium alloys. The investigation was carried out by examining the corroded surfaces of the alloys after potentiodynamic polarization tests in a 3.5% NaCl solution with the aid of a scanning electron microscope, and by analysing the flow of anolyte solution using the scanning vibrating electrode technique. The results revealed that the overall corrosion pathways in the alloys are distinctively different and are influenced by the flow of anolyte solution. Also revealed, was the fact that corrosion propagates in two ways (particularly in the AA5083-O and AA6082-T6 alloys): an overall pathway in the corrosion front (filiform-like pathway in the AA5083 alloy and organized linear pathways in AA6082 alloy); and the crystallographic channelling along the 〈100〉 directions. These are dependent on the grain distinct features of the AA5083-O and AA6082-T6 alloys and are not influenced by the presence of coarse second phase particles in these alloys, compared with the AA2024-T3 alloy, where the corrosion pathways are more dependent on the presence of second phase particles and grain boundary character.     

Comparison of susceptibility to pitting corrosion of AA2024-T4, AA7075-T651 and AA7475-T761 aluminium alloys in neutral chloride solutions using electrochemical noise analysis

The susceptibility to pitting corrosion of AA2024-T4, AA7075-T651 and AA7475-T761 aluminium alloys was investigated in aqueous neutral chloride solution for the purpose of comparison using electrochemical noise measurement. The experimentally measured electrochemical noises were analysed based upon the combined stochastic theory and shot-noise theory using the Weibull distribution function. From the occurrence of two linear regions on one Weibull probability plot, it was suggested that there existed two stochastic processes of uniform corrosion and pitting corrosion; pitting corrosion was distinguished from uniform corrosion in terms of the frequency of events in the stochastic analysis. Accordingly, the present analysis method allowed us to investigate pitting corrosion independently. The susceptibility to pitting corrosion was appropriately evaluated by determining pit embryo formation rate in the stochastic analysis. The susceptibility was decreased in the following order: AA2024-T4 (the naturally aged condition), AA7475-T761 (the overaged condition) and AA7075-T651 (the near-peak-aged condition).     

Effect of combinative addition of Ti and Sr on modification of AA4043 welding wire and mechanical properties of AA6082 welded by TIG welding

To improve the mechanical properties of AA6082 weld welded by tungsten inert gas welding using AA4043 welding wire, the effect of addition of Ti and/or Sr on continuous cast and rolled AA4043 welding wire was investigated. Experimental results indicated that Ti and Sr are excellent modifiers, which improve the microstructure of the AA4043 welding wire and enhance the mechanical properties of the AA6082 weld. It was found that the combinative addition of Ti and Sr can effectively modify both the α(Al) dendrites and eutectic Si phases compared with individual addition of Ti or Sr. In addition, Ti and/or Sr also changed the microstructure of the AA6082 weld. The tensile strength of the AA6082 weld reached the maximum value when 0.08% Ti and 0.025% Sr were added simultaneously. These results indicate that the combinative addition of Ti and Sr can be an effective composite modifier.     

Microstructure of Nitrided Aluminum Alloys Using an Electron-Beam-Excited-Plasma （EBEP）

Nitriding of surface of aluminum alloys was carried out with using an electron-beam-excited-plasma (EBEP) technique. The EBEP is sustained by electron impact ionization with energetic electron beam. Two kinds of substrates,aluminum alloys AA5052 and AA5083, were exposed to the down flow of EBEP source at 843 K for 45min. The specimens were characterized with respect to following properties: crystallographic structure (XRD), morphology (SEM) and the cross sectional microstructures of the nitrided layer was observed using a scanning electron microscopy (SEM). There are some Al2O3 particles on the surface of the nitrided AA5052 and AA5083. The AlN layers were formed on the substrates with the thickness of 4.5μm for AA5052 and 0.5μm for AA5083. A relatively uniform nitrided surface layer composed of AlN can be observed on the AA5052 substrate. The grains size near the interfaces between the substrate and AlN layer were smaller than that near the surface. On the surface of AlN layer, the concentration of nitrogen was high and in the middle of AlN layer it had a constant concentration like the aluminum and the concentration was decreased with approaching to the interface. On the surface of nitrided AA5083, a uniform AlN layer was not formed as the reason for the high nitriding temperature.     

Corrosion Protection of AA2024-T3 by Cerium Malate and Cerium Malate-Doped Sol-Gel Coatings

Cerium malate (CeMal) was tested as a corrosion inhibitor for AA2024-T3 in this work. Corrosion inhibition on bare AA2024-T3 indicated that the inhibiting effect was a result of the synergistic effect of cerium cations and maleic anions. The corrosion of AA2024-T3 was stagnated by greatly reducing the corrosion current when CeMal was present in NaCl solutions. CeMal was adsorbed on the surface of AA2024-T3 forming a protective film in the initial stage. Then, cerium cations transformed to cerium oxide/hydroxides, precipitating on the cathode sites to inhibit the further corrosion. The electrochemical impedance spectra results of the sol-gel coatings proved that CeMal was an effective corrosion inhibitor in the sol-gel coatings to provide corrosion protection for AA2024-T3.