第二相对镁基材料微弧氧化过程的影响机制<sup>*</sup>

doi:10.11900/0412.1961.2015.00500

金属学报

2016, Vol. 52

Issue (6): 689-697 DOI: 10.11900/0412.1961.2015.00500

论文

本期目录 | 过刊浏览

第二相对镁基材料微弧氧化过程的影响机制^*

王艳秋¹(

),吴昆²,王福会^1,³

1 哈尔滨工程大学超轻材料与表面技术教育部重点实验室, 哈尔滨 150001
2 哈尔滨工业大学材料科学与工程学院, 哈尔滨 150001
3 中国科学院金属研究所, 沈阳 110016

EFFECTS OF SECOND PHASES ON MICROARC OXIDATION PROCESS OF MAGNESIUM BASE MATERIALS

Yanqiu WANG¹(

),Kun WU²,Fuhui WANG^1,³

1) Education Ministry Key Laboratory of Superlight Materials and Surface Technology, Harbin Engineering University, Harbin 150001, China
2) School of Materials Science and Engineering, Harbin Institute of Technology, Harbin 150001, China
3) Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

引用本文:

王艳秋,吴昆,王福会. 第二相对镁基材料微弧氧化过程的影响机制^*[J]. 金属学报, 2016, 52(6): 689-697.
Yanqiu WANG, Kun WU, Fuhui WANG. EFFECTS OF SECOND PHASES ON MICROARC OXIDATION PROCESS OF MAGNESIUM BASE MATERIALS[J]. Acta Metall Sin, 2016, 52(6): 689-697.

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摘要:

对含有不同类型第二相的镁基材料进行微弧氧化处理, 研究基体材料第二相对其微弧氧化行为的影响规律及其影响机制. 利用SEM观察第二相在微弧氧化初期阶段的存在状态, 并结合EDS分析第二相的成分及状态变化; 通过不同镁基材料在微弧氧化过程中的电压演变趋势分析第二相对微弧氧化行为的影响. 根据微弧氧化膜的生长原理, 将膜层的生长过程简化等效为一个电容器的反复击穿-重构过程, 并依此讨论了微弧氧化膜的形成过程及第二相的影响机理. 结果表明, 第二相对镁基材料微弧氧化行为的影响与其自身特性密切相关; 在微弧氧化的初期阶段, 第二相是否具备阀金属特性及其导电特性是影响微弧氧化行为的重要因素. 对于具备阀金属特性的第二相, 由于其表面能够形成火花放电所必须的阻挡层, 因此第二相的存在不会对微弧氧化行为产生明显影响. 对于不具备阀金属特性的第二相, 其导电特性决定了镁基材料在微弧氧化初期阶段能否正常发生火花放电并顺利进入膜层生长阶段.

关键词 ：镁合金, 金属基复合材料, 第二相, 微弧氧化, 阻挡层

Abstract：

The effects of second phases on microarc oxidation (MAO, also named plasma electrolytic oxidation-PEO) behavior of Mg base materials were investigated and the related mechanism was discussed. The formation of barrier layer and its influence on sparking discharge behavior were characterized and analyzed on the base of systematic selecting and designing substrate materials. The variation of second phases at the early MAO stage was observed and analyzed by SEM and EDS, and then the effect mechanism of second phases on MAO behaviors was revealed. Voltage evolution trend during MAO were recorded to study the formation state of the barrier layer on the different Mg base materials. According to the growth mechanism of MAO film, the film growth process can be simplistically considered as a repeated breakdown and reconstruction process of a capacitor. Accordingly, the growth process of MAO film on multiphase metal materials and the effects of second phases were discussed. The results show that different second phases in substrate materials have different effects on formation process of MAO films, depending on their own characteristics. For the second phases which have the characteristics of valve metals, although selective sparking discharge occurs at the early stage of MAO, the second phases will not hinder the growth of MAO film since barrier layer can form on the second phases, and they will not induce structural defects into the film-substrate interface. If the second phases have not the characteristics of valve metals, their conductivity property will be an important influencing factor to affect the MAO behaviors. For the elecinsulating second phases which have not the characteristics of valve metals, sparking discharge just occurs on Mg matrix in the substrate, while doesn't occur on the second phases; the second phases exist in the MAO film as heterogeneous phases, do not react in MAO process, and will not hinder the growth of MAO film. For the semi-conductive second phases which have not the characteristics of valve metals, they delay the growth of MAO film because they destroy the integrity of barrier layer. For the electroconductive second phases which have not the characteristics of valve metals, they seriously hinder the growth of MAO film.

Key words： magnesium alloy metal matrix composite second phase microarc oxidation barrier layer

收稿日期: 2015-09-25

基金资助:* 国家自然科学基金项目51001036和国家国际科技合作专项项目2014DFR50560资助

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https://www.ams.org.cn/CN/10.11900/0412.1961.2015.00500 或 https://www.ams.org.cn/CN/Y2016/V52/I6/689

图1 铸态AZ91D镁合金的SEM像

图2 AZ91D镁合金微弧氧化初期形貌的SEM像

图3 Al18B4O33w/AZ91D镁基复合材料微弧氧化初期形貌的SEM像

图4 SiCw/AZ91D镁基复合材料微弧氧化初期形貌的SEM像

图5 SiCw/AZ91D镁基复合材料微弧氧化60 s时表面不同部位的EDS结果

图6 (Cf+Al18B4O33w)/AZ91D复合材料在微弧氧化处理前后表面形貌的SEM像

图7 不同镁基材料在恒电流模式下进行微弧氧化处理时的电压随时间变化曲线

图8 微弧氧化膜形成原理示意图

表1 镁基材料在微弧氧化初期的电压升高速率R和稳态电压U随电流密度的变化

[1]	Van T B, Brown S D, Wirtz G P.Ceram Bull, 1977; 56: 563
[2]	Ikonopisov S.Electrochim Acta, 1977; 22: 1077
[3]	Srinivasan P B, Liang J, Blawert C, Stormer M, Dietzel W.Appl Surf Sci, 2009; 255: 4212
[4]	Li X J, Cheng G A, Xue W B, Zheng R T, Cheng Y J.Mater Chem Phys, 2008; 107: 148
[5]	Wang Y M, Lei T Q, Jiang B L, Guo L X.Appl Surf Sci, 2004; 233: 258
[6]	Verdier S, Boinet M, Maximovitch S, Dalard F.Corros Sci, 2005; 47: 1429
[7]	Krishtal M M.Met Sci Heat Treat, 2004; 46: 378
[8]	Khaselev O, Weiss D, Yahalom J.Corros Sci, 2001; 43: 1295
[9]	Khaselev O, Yahalom J.Corros Sci, 1998; 40: 1149
[10]	Hsiao H Y, Tsai W T.J Mater Res, 2005; 20: 2763
[11]	Zhu Q Z, Xue W B, Lu L, Du J C, Liu G J, Li W F.Acta Metall Sin, 2011; 47: 74
[11]	(朱庆振, 薛文斌, 鲁亮, 杜建成, 刘贯军, 李文芳. 金属学报, 2011; 47: 74)
[12]	Xue W B.Appl Surf Sci, 2006; 252: 6195
[13]	Xue W B, Wu X L, Li X J, Tian H.J Alloys Compd, 2006; 425: 302
[14]	Xue W B, Jin Q, Zhu Q Z, Hua M, Ma Y Y. J Alloys Compd, 2009; 482: 208
[15]	Arrabal R, Matykina E, Skeldon P, Thompson G E.Appl Surf Sci, 2009; 255: 5071
[16]	Arrabal R, Pardo A, Merino M C, Mohedano M, Casajús P, Matykina E, Skeldon P, Thompson G E. Corros Sci, 2010; 52: 3738
[17]	Hihara L H, Latanision R M.Int Mater Rev, 1994; 39: 245
[18]	Trzaskoma P P, McCafferty E, Crowe C R.J Electrochem Soc, 1983; 130: 1804
[19]	Pohlman S L.Corrosion, 1978; 34: 156
[20]	Turhan M C, Li Q Q, Jha H, Singer R F, Virtanen S.Electrochim Acta, 2011; 56: 7141
[21]	Xue W B.Acta Metall Sin, 2006; 42: 350
[21]	(薛文斌. 金属学报, 2006; 42: 350)
[22]	Wang Y Q, Wang X J, Zhang T, Wu K, Wang F H.J Mater Sci Technol, 2013; 29: 1129
[23]	Wang Y Q, Wang X J, Wu K, Wang F H.J Mater Sci Technol, 2013; 29: 267
[24]	Wang Y Q, Wang X J, Gong W X, Wu K, Wang F H.Appl Surf Sci, 2013; 283: 906
[25]	Liu R, Weng N, Xue W B, Hua M, Liu G J, Li W F. Surf Coat Technol, 2015; 269: 212

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