Effects of MgO Modified HA Nanoparticles on the Microstructure and Properties of Mg-Zn-Zr/m-HA Composites

doi:10.11900/0412.1961.2017.00249

Acta Metall Sin

2017, Vol. 53

Issue (10): 1364-1376 DOI: 10.11900/0412.1961.2017.00249

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Effects of MgO Modified HA Nanoparticles on the Microstructure and Properties of Mg-Zn-Zr/m-HA Composites

Haoran ZHENG¹, Minfang CHEN^1,²(

), Zhen LI¹, Chen YOU¹, Debao LIU¹

1 School of Materials Science and Engineering, Tianjin University of Technology, Tianjin 300384, China
2 Tianjin Key Lab for Photoelectric Materials & Devices, Tianjin University of Technology, Tianjin 300384, China

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Haoran ZHENG, Minfang CHEN, Zhen LI, Chen YOU, Debao LIU. Effects of MgO Modified HA Nanoparticles on the Microstructure and Properties of Mg-Zn-Zr/m-HA Composites. Acta Metall Sin, 2017, 53(10): 1364-1376.

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Abstract

Magnesium metal matrix composites (MMCs) are hot research spots in recent years because of their adjustable mechanical and corrosion properties. However, the agglomerate particles in MMCs limit its applications in many areas. In order to solve this problem, MgO surface modified hydroxyapatite ceramic nanorods (m-HA) were prepared and added as reinforcement in this work. Mg-3Zn-0.8Zr alloy (MZZ), Mg-3Zn-0.8Zr composites with unmodified (MZZH) and modified (MZZMH) nanorods were produced by high shear mixing technology. Effects of m-HA nanorods on the microstructure, mechanical properties and corrosion properties of Mg-Zn-Zr/m-HA composites were investigated. The results showed that the addition of HA nanorods refined the grain size of MZZ alloy and gave a raise to the mechanical properties and electrochemical corrosion resistance of MZZ alloy. The grain size of MZZMH was smaller than that of MZZH and the distribution of m-HA nanorods in the matrix was more uniform than that of HA nanorods. Moreover, the as-extruded MZZMH composite exhibited a yield tensile strength of 291 MPa and ultimate tensile strength of 325 MPa, greater than that of MZZH. The corrosion potential of MZZMH was approximately 59 mV greater than that of MZZH. The corrosion rate of MZZMH was 5 mm/a after immersion 7 d in SBF, lower than that of MZZH. The corrosion resistance of MZZMH was better than that of MZZH due to the different corrosion mechanism. Surface corrosion products of MZZMH was alternating Mg(OH)₂ and Ca-P compound at the early stage of immersion, but surface corrosion layer of MZZH specimen was always Mg(OH)₂. The mechanical properties and corrosion resistance of Mg-Zn-Zr/m-HA composites were improved by the addition of m-HA.

Key words: MgO coated HA nanoparticle magnesium matrix composite microstructure mechanical property corrosion property

Received: 26 June 2017

ZTFLH:

TB333

Fund: Supported by National Natural Science Foundation of China (No.51371126), Major Science and Technology Projects of Tianjin (No.15ZXQXSY00080) and Science and Technology Developing Foundation of Tianjin High Education (No.20110301)

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	Haoran ZHENG
	Minfang CHEN
	Zhen LI
	Chen YOU
	Debao LIU

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https://www.ams.org.cn/EN/10.11900/0412.1961.2017.00249 OR https://www.ams.org.cn/EN/Y2017/V53/I10/1364

Fig.1 XRD spectra of MgO, HA and modified HA (m-HA)

Fig.2 TEM images (a, b) and EDS (c, d) of m-HA (a, c) and HA (b, d) nanoparticles (Insets in Figs.2a and b are enlarged images, W—mass fraction, A—atomic fraction)

Fig.3 OM images of as-cast Mg-3Zn-0.8Zr/1m-HA (MZZMH) (a), Mg-3Zn-0.8Zr/1HA (MZZH) (b) and Mg-3Zn-0.8Zr (MZZ) (c)

Fig.4 Cooling curves for MZZ and MZZH (a) and corresponding enlarged curves (b) (?T—degree of under cooling, T_L—actual solidification temperature)

Fig.5 OM (a, d) and SEM images (b, c, e, f) of as-extruded MZZMH (a~c) and MZZH (d~f)

Fig.6 Hardness (a) and tensile properties (b) of MZZMH和MZZH composites (UTS—ultimate tensile strength, YTS—yield tensile strength)

Fig.7 Tafel polarization curves of as-extruded MZZMH, MZZH composites and MZZ alloy (i_corr—corrosion current)

Table 1 Electrochemical parameters of MZZMH, MZZH and MZZ in simulated body fluid (SBF) acquired from the polarization test and EIS

Fig.8 EIS (a) and equivalent circuit (b~d) of as-extruded MZZMH (b), MZZH (c) composites and MZZ (d) alloy (R_s—solution resistance, R₁—charge transfer resistance, R₂—corrosion product layer resistance, R₃—mass transfer resistance, R_L—corresponding resistance of inductance components, CPE—equivalence element, C—capacitance, L—inductance element)

Fig.9 OM images (a1~a4, b1~b4) and SEM images (c1~c4, d1~d4) of surface morphologies in MZZMH (a1~a4, c1~c4) and MZZH (b1~b4, d1~d4) before (a1~a4, b1~b4) and after (c1~c4, d1~d4) removing the corrosion products for immersion 1 d (a1~d1), 3 d (a2~d2), 5 d (a3~d3), 7 d (a4~d4) in SBF

Fig.10 Curves of pH (a), hydrogen evolution (b) and corrosion rate (c) of as-extruded MZZMH and MZZH after immersed in SBF

Fig.11 Surface morphologies (a~g) and EDS (h) of MZZH for immersion 1 h (a), 2 h (b), 4 h (c, h), 5 h (d), 6 h (e), 3 d (f) and 5 d (g) in SBF

Fig.12 Surface morphologies (a~j) and EDS (k, l) of MZZMH for immersion 1 h (a), 1.5 h (b), 2 h (c), 2.5 h (d, k), 4 h (e), 5 h (f), 6 h (g, l), 1 d (h), 3 d (i) and 5 d (j) in the SBF

Fig.13 Corrosion mechanism of MZZMH (a, b) and MZZH (c, d) immersed in SBF(a) galvanic corrosion in MZZMH(b) formation of the alternative protective film of Mg(OH)₂ and Ca-P particles(c) galvanic corrosion in MZZH(d) formation of Mg(OH)₂ layer

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