Startseite Effects of NiO content on the microstructure and mechanical properties of AgSnO2NiO composites
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Effects of NiO content on the microstructure and mechanical properties of AgSnO2NiO composites

  • Xiaolong Zhou EMAIL logo , Li Chen , Manmen Liu , Jie Yu , Damin Xiong , Zhong Zheng und Lihui Wang
Veröffentlicht/Copyright: 11. Mai 2019
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Science and Engineering of Composite Materials
Aus der Zeitschrift Science and Engineering of Composite Materials Band 26 Heft 1

Abstract

The AgSnO2NiO composites were prepared by internal oxidation method. The effects of different NiO content on the microstructure and mechanical properties of AgSnO2NiO composites were studied. The phase structure and surface morphology of the prepared AgSnO2NiO materials were characterized by X-ray Diffraction (XRD), Scanning Electron Microscopy (SEM) and Metallographic Microscopy (MM). The results showed that the AgSnO2NiO composites with different NiO content can be obtained by the process of preoxidation of AgSn alloy powder and internal oxidation of ingot containing Ni. The agglomeration phenomenon of Ni in the silver matrix was serious, which led to the agglomeration of in-situ generated NiO particles after internal oxidation. After the multi-pass drawing, the SnO2 particles dispersedly distributed in the AgSnO2NiO composites and the NiO particles gradually dispersed from the agglomerated state of the sintered ingot billet. The hardness of the prepared AgSnO2NiO composites increased slightly with the increase of NiO content. The mechanical properties test showed that the introduction of NiO particles significantly improved the tensile strength and elongation of AgSnO2 materials to a certain degree. Adding proper amount of NiO is beneficial to improve the overall performance of AgSnO2 materials.

Keywords: Internal oxidation; AgSnO2NiO composites; Microstructure and mechanical properties

1 Introduction

Silver-metal oxide (AgMeO) electrical contact materials is widely used in the industrial production of control switches, relays, connectors and switch breakers for household appliances that are common in daily life [1, 2, 3]. Among them, Silver-cadmium oxide (AgCdO), which is known as “universal electrical contact material”, has been firmly occupying the commanding height of the electrical contact material market for decades because of its low and stable contact resistance, small amounts of arc erosion and excellent resistance towelding [4, 5]. However, the Cd element in AgCdO is highly toxic, causing great pollution to the human body and the environment. Silver-tin oxide (AgSnO2) is considered to be one of the most promising new environmentally friendly electrical contact materials to substitute AgCdO [6, 7, 8]. AgSnO2 has the advantages of excellent anti-welding properties, arc erosion resistance and good resistance to mechanical wear, but it also has its shortcomings. The wettability between Ag and SnO2 is poor and SnO2 is a semiconductor. Under the multiple actions of the arc, the SnO2 particles with lower density will be concentrated on the surface of the molten Ag, resulting in increased contact resistance and large temperature rise, which greatly reduces the electrical performance of the material [9, 10]. Moreover, the low interfacial bonding strength between the harder SnO2 and the softer Ag leads to the poor plasticity and ductility of the AgSnO2 electrical contact materials, and therefore, it is relatively difficult to processing and forming [11, 12].

Up to now, the preparation methods of AgSnO2 electrical contact materials mainly include Internal Oxidation (I/O) and Powder Metallurgy (P/M) [13]. The particles produced by I/O are fine and distributed uniformly, while the materials produced by P/M have agglomeration phenomenon, the particle size is larger , and the distribution is uneven. Compared with the powder metallurgy method,

the AgSnO2 electrical contact material produced by the internal oxidation method has better processability and arc erosion resistance [14, 15]. Furthermore, the addition of different metal oxides such as CuO, In2O3, etc., and oxides of rare earth elements (La2O3, CeO2, etc.) can effectively improve the wettability between Ag and SnO2, thereby reducing the contact resistance and temperature rise during arcing [16, 17, 18, 19]. Wang J et al [20] found that CuO-doped AgSnO2 material has denser microstructure, higher hardness, and better arc erosion resistance than AgSnO2 materials. The arc erosion test indicated that the introduction of CuO can significantly inhibit the spatter loss of molten Ag during the welding process. Chen J et al [21] studied the molten bridge phenomenon of the AgSnO2In2O3 electrical contact material and found that In2O3 can restrain the transfer of Ag, which plays a protective role for the material. Zhang L et al [22] used powder metallurgy method to prepare AgSnO2La2O3 electrical contact materials with excellent resistance to welding. The results showed that La2O3 can increase the viscosity of melt pool to and improve the wettability between Ag and SnO2. However, there has been no report about the addition of NiO to AgSnO2 composites. Interestingly, the AgNi electrical contact material has a lower contact resistance than AgSnO2, but its mechanical strength and anti-welding performance are far inferior to AgSnO2 [23, 24].

In order to combine the advantages of both AgSnO2 and AgNi electrical contact materials and to obtain a uniform microstructure of fine particles, AgSnO2NiO composites were prepared by internal oxidation combined with high temperature sintering. NiO particles were formed in situ on the surface of the Ag matrix during the sintering process. In this paper, the effects of NiO content on the microstructure and mechanical properties of AgSnO2NiO composites were studied. The result can provide a useful reference for the compound modification method between different silver-metal oxide electrical contact materials.

2 Experimental procedures

2.1 Raw materials and composition proportion

The raw materials used in this experiment and the requirement of purity and particle size are as follows: Ag powder (purity ≥ 99.99%, particle size of 40-50 μm), Ni powder (purity ≥ 99.5%, particle size of 40-50 μm), AgSn alloy powder (purity ≥ 99.99%, particle size of 40-50 μm). The required raw materials and amounts were given in Table 1.

Table 1

The amounts of raw materials to prepare 200g AgSnO2NiO ingot

Preparation methodSample numberIngot billet (wt%)Ag powder(g)AgSn alloy powder(g)Ni powder(g)
Internal oxidation1# sampleAgSnO2(5)NiO(0.5)143.5153.3670.786
and2# sampleAgSnO2(5)NiO(1.0)142.5153.3671.572
high-temperature3# sampleAgSnO2(5)NiO(1.5)141.5153.3672.358
sintering4# sampleAgSnO2(5)NiO(2.0)140.5153.3673.144

2.2 Preparation of AgSnO2NiO composites

2.2.1 Pre-oxidation treatment of AgSn alloy powder

The AgSn alloy powder was tiled on corundum. The pre-oxidation temperature was gradually raised from room temperature to 373 K for 1 h, 473 K for 1 h, 673K for 2 h, and 1073 K for 4 h.

2.2.2 Internal oxidation of ingot billet containing Ni and processing of AgSnO2NiO composites

First of all, the Ag, AgSnO2 and Ni powders were put into a planetary ball mill (QM-ISP2) for ball milling and mixing at 1000 rad/min for 5 h. Then, the uniformly mixed alloy powder was placed in a cold press mold and pressed into an alloy biscuit under the pressure of 20MPa for 2 min. The obtained biscuit with a diameter of 27 mm was placed in a box furnace and sintered in an oxygen-containing atmosphere. The sintering process was similar to pre-oxidation treatment. Maintain a sufficiently long sintering time, so that Ni was completely oxidized to obtain in-situ NiO particles. The prepared AgSnO2NiO composites were repressed under the pressure of 50 MPa for 5 min and re-sintered at 1093 K. Finally, the wire was obtained by extrusion and drawing.

2.3 Characterization

The phase structure of the prepared AgSnO2NiO composites was analyzed by a Bruker D8 advanced X-ray Diffraction (XRD). The surface morphology, element distributions and fracture morphology of the AgSnO2NiO composites were characterized by a Tescan VEGA-3SBH tungsten filament Scanning Electron Microscope (SEM) coupled with Energy Dispersion Spectrometer (EDS). The microstructures of AgSnO2NiO ingot billets and wires were observed and investigated by a ZEISS Scope.A1 Metallographic Microscope (MM). The hardness at different processing stage was tested on a MC010 series microhardness tester under the load of 50 g for 15 s. Hardness value was the average of the measured values at the 5 test points of the sample. After the drawn wire was annealed, a tensile test was performed using an AG-IS type 10KN universal testing machine at a tensile speed of 0.5 mm/min to obtain tensile strength and elongation results.

3 Results and discussion

3.1 Effects of NiO content on the microstructure of AgSnO2NiO composites

Figure 1 shows the XRD pattern of the AgSnO2NiO composites with NiO content of 2% prepared by internal oxidation. It can be seen that only Ag, SnO2 and NiO phases were contained in the composite after internal oxidation, indicating that the AgSnO2NiO composite can be successfully prepared by the internal oxidation method.

Figure 1 XRD pattern of AgSnO2NiO composites with NiO content of 2%
Figure 1

XRD pattern of AgSnO2NiO composites with NiO content of 2%

Figure 2 shows the surface morphology of the AgSnO2NiO composites with NiO content of 2% and the corresponding energy spectrum analysis of region A, B, C and D. It can be seen that agglomeration of NiO particles occurred in the prepared composites. Figure 2b shows the morphology of the four marked regions more intuitively. The energy spectrum analysis of region A and B showed that there were a small amount of Ag and SnO2 among NiO particles. It is noteworthy that only SnO2 and NiO exist in region D, indicating that the black material in the wrapping layer outside the agglomerated NiO is SnO2.

Figure 2 Surface morphology of the AgSnO2NiO composites and corresponding energy spectra: (c) region A; (d) region B; (e) region C; (f) region D;
Figure 2

Surface morphology of the AgSnO2NiO composites and corresponding energy spectra: (c) region A; (d) region B; (e) region C; (f) region D;

Figure 3 shows the metallographic structure of the AgSnO2NiO biscuit and the sintered ingot billet after internal oxidation with NiO content of 2%. There was a clear difference between the biscuit and the sintered ingot billet in area A. The area A in Figure 3a was a light gray round spot (pure Ni powder particles), while it was dark gray and there was a circle of black structure around it (a mixture of SnO2 and NiO particles) in Figure 3b The result indicated that the internal oxidation of Ni generated NiO through high-temperature sintering. Comparing Figure 3a with Figure 3b it was shown that the agglomerated Ni in the biscuit hardly diffused during the internal-oxidation sintering, and the NiO was basically generated in-situ, which is caused by the immiscibility of Ag and Ni. Therefore, with the increase of Ni content, the agglomeration of Ni in the silver matrix will be more serious, eventually leading to serious agglomeration of NiO particles after internal oxidation, and the size of NiO particles generated is larger. In addition, the areas B in Figure 3a and Figure 3b were both ring structures in which SnO2 particles surround the Ag matrix. It can be deduced that the Sn diffused to the surface of AgSn particle and reacted with oxygen to generate SnO2 particles during the pre-oxidation of the AgSn alloy powder.

Figure 3 Microstructure of AgSnO2NiO ingot billet × 500; (a) biscuit; (b) sintered ingot billet;
Figure 3

Microstructure of AgSnO2NiO ingot billet × 500; (a) biscuit; (b) sintered ingot billet;

Figure 4 shows the horizontal microstructure metallography diagram of the wire after extrusion and drawing of the AgSnO2NiO composites with NiO content of 2%. It was found that the smaller SnO2 particles dispersedly distributed in Ag matrix and the larger NiO particles were present in the Ag matrix mainly in the state of particle agglomeration. With the increase of plastic deformation, it was not obvious that the agglomerated NiO particles were completely dispersed.

Figure 4 Horizontal microstructure metallography of AgSnO2NiO after extrusion and drawing × 200 (a) extrusion rod diameter of 6.0 mm; (b) wire drawing diameter of 5.2 mm; (c) wire drawing diameter of 3.4 mm; (d) wire drawing diameter of 1.5 mm
Figure 4

Horizontal microstructure metallography of AgSnO2NiO after extrusion and drawing × 200 (a) extrusion rod diameter of 6.0 mm; (b) wire drawing diameter of 5.2 mm; (c) wire drawing diameter of 3.4 mm; (d) wire drawing diameter of 1.5 mm

Figure 5 shows the vertical microstructure metallographic diagram of the wire after extrusion and drawing of AgSnO2NiO composites with NiO content of 2%. It was known that dark grey and larger agglomerates in the area A was NiO particles, and the area B are linearly-arranged SnO2 particles which are gradually dispersed along the extrusion and drawing directions, as is shown in Figure 5a

Figure 5 Vertical microstructure metallography of AgSnO2NiO after extrusion and drawing × 200 (a) extrusion rod diameter of 6.0 mm (b) wire drawing diameter of 5.2 mm (c) wire drawing diameter of 3.4 mm (d) wire drawing diameter of 1.5 mm
Figure 5

Vertical microstructure metallography of AgSnO2NiO after extrusion and drawing × 200 (a) extrusion rod diameter of 6.0 mm (b) wire drawing diameter of 5.2 mm (c) wire drawing diameter of 3.4 mm (d) wire drawing diameter of 1.5 mm

b and c. With the increase of drawing passes, the distribution of SnO2 particles became more uniform, as shown in Figure 5d and the NiO particles were partially dispersed, as shown in areas A in Figure 5b and c On the whole, since the size of NiO particles was much larger than that of SnO2 particles, it is difficult to be completely dispersed, resulting in its uneven distribution in the Ag matrix.

Figure 6 shows the fracture surface of the wire (diameter of 1.3 mm) after extrusion and drawing. It can be seen that dimples of different sizes were formed in the fracture center of the four kinds of AgSnO2NiO wires, and there is no obvious large granular structure in the dimples, indicating that the agglomerated NiO particles were gradually dispersed during the plastic deformation process. Moreover, it also indicates that the fracture mode of the samples was ductile fracture, which means that the prepared composites have good processing properties.

3.2 Effects of NiO content on the mechanical properties of AgSnO2NiO composites

Figure 7 shows the change trends of the microhardness of the AgSnO2NiO composites during the processing. It can be seen that the microhardness values of AgSnO2NiO drawn wire were all higher than 105 HV and the NiO content has little effect on the microhardness. When the AgSnO2NiO composites with NiO content of 2%was drawn into a wire with a diameter of 1.5mm, the microhardness reached a maximum of 125.03 HV. The reason is that the SnO2 particles are completely dispersed, and the agglomerated NiO particles are partially dispersed, which together play a dispersion strengthening role.

Figure 8 shows the change trends of elongation and tensile strength when the AgSnO2NiO composites with different NiO content were drawn into a wire with a diameter of 1.30 mm. It can be seen that the NiO content has no significant effect on the tensile strength of AgSnO2NiO (maintained

Figure 6 Fracture morphology of AgSnO2NiO after extrusion and drawing × 5000 (a) 1# sample AgSnO2(5)NiO(0.5); (b) 2# sample AgSnO2(5)NiO(1.0); (c) 3# sample AgSnO2(5)NiO(1.5); (d) 4# sample AgSnO2(5)NiO(2.0)
Figure 6

Fracture morphology of AgSnO2NiO after extrusion and drawing × 5000 (a) 1# sample AgSnO2(5)NiO(0.5); (b) 2# sample AgSnO2(5)NiO(1.0); (c) 3# sample AgSnO2(5)NiO(1.5); (d) 4# sample AgSnO2(5)NiO(2.0)

Figure 7 Change trends of microhardness after processing
Figure 7

Change trends of microhardness after processing

Figure 8 The chart of AgSnO2NiO samples’ elongation and tensile strength
Figure 8

The chart of AgSnO2NiO samples’ elongation and tensile strength

at about 175 MPa), but it has a significant effect on the elongation.When the content of NiO was 1%, the tensile strength of the wire is the highest (178.873MPa), and the elongation r is also the best (6.2%).

4 Conclusions

  1. The microstructure characteristics of AgSnO2NiO composites prepared by internal oxidation method were as follows: SnO2 distributed in an annular shape around the Ag matrix, and the NiO was in agglomerated distribution. The agglomeration of NiO is related to the agglomeration of Ni before internal oxidation.

  2. After extrusion and multi-pass drawing process, the oxide particles dispersedly distributed in the Ag matrix. The SnO2 particles are linearly arranged in the Ag matrix in a like-fibrous shape along the extrusion and drawing direction. However, with the increase of plastic deformation, agglomerated NiO particles can be partially dispersed. But it is difficult to completely disperse the NiO particles.

  3. NiO content has no significant effect on the tensile strength of AgSnO2NiO composites, but it has an important influence on the elongation. When the content of NiO was 1%, the tensile strength and elongation of the AgSnO2NiO composites reached a maximum of 178.873MPa and 6.2%.

  4. The preparation process has a significant effect on the microhardness ofAgSnO2NiO composites.When the AgSnO2NiO composites with NiO content of 2% was drawn into a wire with a diameter of 1.5mm, the microhardness reached a maximum of 125.03 HV. The reason is that defects such as pits and holes inside the material gradually decreased with the process of repressing-resintering, drawing, and extrusion. In addition, with the increase of drawing passes, SnO2 and NiO particles are gradually dispersed and uniformly distribute in the Ag matrix, which play a role in dispersion strengthening.

Acknowledgements

We gratefully thank for the Key Project of Natural Science Foundation of Yunnan Province, China (GrantNO. 2017FA027), the National Natural Science Foundation of China (Grant NO. 51361016), the Scientific Research Fund Project of Yunnan Provincial Department of Education, China (Grant NO. 2016YJS030), the Analysis and Testing Foundation of Kunming University of Science and Technology (No. 2018M20172130029) and the Natural Science Foundation of Yunnan Province, China (Grant NO. 2016FB092).

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Received: 2018-09-05
Accepted: 2018-12-08
Published Online: 2019-05-11
Published in Print: 2019-01-28

© 2019 X. Zhou et al., published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 Public License.

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https://doi.org/10.1515/secm-2019-0005
Schlagwörter für diesen Artikel
Internal oxidation; AgSnO2NiO composites; Microstructure and mechanical properties
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  14. The influence of the WC-Co composite microstructure model on stress field heterogeneity at the microstructure level: FEM based study
  15. Vibration-damping characterization of the basalt/epoxy composite laminates containing graphene nanopellets
  16. A review on nanocomposite hydrogels and their biomedical applications
  17. Optimization and simulation analysis of structure parameters of OPCM ultrasonic longitudinal wave actuating element
  18. Research Article
  19. Preparation of POSS-triol/wollastonite composite particles by Liquid phase mechanochemical method and its application in UV curable coatings
  20. Research on preload relaxation for composite pre-tightened tooth connections
  21. Dough moulding compound reinforced silicone rubber insulating composites using polymerized styrene butadiene rubber as a compatibilizer
  22. Hydration And Microstructure Of Astm Type I Cement Paste
  23. Effects of NiO content on the microstructure and mechanical properties of AgSnO2NiO composites
  24. Overall buckling behaviour of laminated CFRP tubes with off-axis ply orientation in axial compression
  25. UV sensing optode for composite materials environment monitoring
  26. On crushing characteristics of hybrid sandwich aluminum-cardboard panels reinforced with glass fiber composite rods
  27. Preparation and characterization of Ni-Cu composite nanoparticles for conductive paints
  28. A research on the preparation of oil-adsorbing hydrophobic porous resins by high internal phase emulsions (HIPEs) template
  29. Material characteristics of random glass-mat-reinforced thermoplastic under cryogenic thermal cycles
  30. Differentiation of non-black fillers in rubber composites using linear discriminant analysis of principal components
  31. Research Article
  32. Efficiency of TiO2 catalyst supported by modified waste fly ash during photodegradation of RR45 dye
  33. Synthesis and performance of polyurethane/silicon oxide nano-composite coatings
  34. Study on preparation of magnesium-rich composite coating and performance enhancement by graft modification of epoxy resin
  35. Research Article
  36. Mechanical and wear properties of polyetheretherketone composites filled with basalt fibres
  37. Mechanical Properties of Al 25 wt.% Cu Functionally Graded Material
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  39. Weight reduction of a carbon fibre composite wheel
  40. Synthesis, electrical properties, and kinetic thermal analysis of polyaniline/ polyvinyl alcohol - magnetite nanocomposites film
  41. Seismic Behaviour of TRC-Strengthened RC Columns under Different Constraint Conditions
  42. Characterization of neat and modified asphalt binders and mixtures in relation to permanent deformation
  43. Microstructures, interface structure and room temperature tensile properties of magnesium materials reinforced by high content submicron SiCp
  44. Research Article
  45. Effect of Cutting Temperature on Bending Properties of Carbon Fibre Reinforced Plastics
  46. Mechanical and tribological properties of B-C-N coatings sliding against different wood balls
  47. Thermal conductivity of unidirectional composites consisting of randomly dispersed glass fibers and temperature-dependent polyethylene matrix
  48. Effects of Waste Eggshells addition on Microstructures, Mechanical and Tribological Properties of Green Metal Matrix Composite
  49. Investigation of porosity effect on flexural analysis of doubly curved FGM conoids
  50. Review Article
  51. Utilization of tailings in cement and concrete: A review
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  53. Equivalent stiffness prediction and global buckling analysis using refined analytical model of composite laminated box beam
  54. Mechanochemical synthesis of zincite doped with cadmium in various amounts
  55. Size-dependent vibration analysis of graphene-PMMA lamina based on non-classical continuum theory
  56. Automated, Quality Assured and High Volume Oriented Production of Fiber Metal Laminates (FML) for the Next Generation of Passenger Aircraft Fuselage Shells
  57. Research Article
  58. An investigation of the stitching effect on single lap shear joints in laminated composites
  59. The low-velocity impact and compression after impact (CAI) behavior of foam core sandwich panels with shape memory alloy hybrid face-sheets
  60. Effect of granulometric distribution on electromagnetic shielding effectiveness for polymeric composite based on natural graphite
  61. The enhancement of filament winding in marine launching rubber gasbag
  62. Research on ELID Grinding Mechanism and Process Parameter Optimization of Aluminum-Based Diamond Composites for Electronic Packaging
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Heruntergeladen am 10.9.2025 von https://www.degruyterbrill.com/document/doi/10.1515/secm-2019-0005/html
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