the influence of hybrid composites structure on their tribological
Transkrypt
the influence of hybrid composites structure on their tribological
14: 1 (2014) 18-22 Andrzej Posmyk1, Jerzy Myalski2 1 Silesian University of Technology, Faculty of Transport, ul. Krasińskiego 8, 40-019 Katowice, Poland University of Technology, Faculty of Materials Engineering and Metallurgy, ul. Krasińskiego 8, 40-019 Katowice, Poland * Corresponding author: E-mail: [email protected] 2 Silesian Received (Otrzymano) 1.02.2014 THE INFLUENCE OF HYBRID COMPOSITES STRUCTURE ON THEIR TRIBOLOGICAL PROPERTIES The paper presents the influence of a hybrid composite structure containing two reinforcing phases i.e. porous, spherical Al2O3 ceramic particles, coated with glassy carbon film which carries out the function of solid lubricant. This composite is manufactured by a new method developed in 2013, which consists of three stages i.e. pre-form manufacturing from porous foam by means of gelcasting, foam saturation with a glassy carbon precursor and its pyrolysis, followed by the infiltration of the pre-form coated with glassy carbon by a liquid alloy. The new method helps to obtain composites with homogenous glassy carbon distribution which improves their tribological properties. The presence of aluminum oxide increases the hardness locally whereas the presence of glassy carbon mitigates the shear strength. Comparative tribological studies of a composite with an AC-AlCu3Mg1 matrix alloy containing 10% Al2O3 and the hybrid composite in which aluminum oxide spheres have been coated with glassy carbon, both sliding against GJL-300 cast iron in air, confirmed the positive influence of carbon on both the friction coefficient and wear. The friction coefficient at a sliding speed of v = 2.5 m/s and unit pressure p = 2 MPa after wearing-in of the sliding surfaces is 0.08÷0.12 for the composites with glassy carbon and 0.25÷0.32 for the composite which contains only ceramic spheres. Keywords: hybrid composite, structure, alumina, glassy carbon, tribological properties, solid lubricant WPŁYW STRUKTURY KOMPOZYTÓW HYBRYDOWYCH NA ICH WŁAŚCIWOŚCI TRIBOLOGICZNE Przedstawiono wpływ struktury kompozytu hybrydowego zawierającego dwie fazy zbrojące, tj. porowate, sferoidalne, puste wewnątrz cząstki Al2O3 jako umocnienie pokryte warstewką węgla szklistego, pełniącego funkcję smaru stałego. Kompozyt ten jest wytwarzany według nowej metody opracowanej w 2013 roku. Metoda składa się z trzech etapów, tj. wytwarzania preformy z porowatej pianki metodą Ŝelowania spienionej zawiesiny, nasączania tej pianki prekursorem węgla szklistego i jego pirolizy oraz infiltracji ciekłym stopem osnowy pokrytej węglem szklistym preformy. Dzięki tej metodzie uzyskuje się zupełnie inną strukturę kompozytu niŜ dotychczasową metodą mieszania. Podczas mieszania uzyskuje się kompozyt o niezbyt równomiernym rozłoŜeniu węgla szklistego, przez co na powierzchni biorącej udział w tarciu moŜna znaleźć obszary o mniejszej zawartości węgla, co sprzyja lokalnemu sczepianiu adhezyjnemu z współpracującym ślizgowo Ŝeliwem. Według nowej metody, uzyskuje się kompozyt z bardziej równomiernym rozłoŜeniem węgla szklistego, co poprawia właściwości tribologiczne. Obecność tlenku glinu zwiększa lokalnie twardość, a węgla szklistego zmniejsza wytrzymałość na ścinanie. Doboru materiałów fazy zbrojącej dokonano zgodnie z hipotezą tarcia opracowaną przez Ernsta i Merchanta, wg której w strefie tarcia powinny być dwa materiały, tj. jeden o duŜej twardości, a drugi o małej wytrzymałości na ścianie. Węgiel szklisty cechuje się małą wytrzymałością na ścianie (30÷50 MPa) i duŜą mikrotwardością porównywalną do SiC (230÷340 HV - SIGRADUR), co zmniejsza siły tarcia. Cechy stereologiczne sfer ceramicznych, takie jak udział powierzchniowy (ilość cząstek na 1 mm2) i średnia średnica decydują o ilości i sposobie rozmieszczenia węgła osadzonego na wewnętrznych i zewnętrznych ściankach sfer. Regulując intensywność i czas osadzania prekursora węglowego na podłoŜu ceramicznym, moŜna dobrać ilość fazy węglowej tworzącej się na ściankach tych sfer ceramicznych. WydłuŜenie czasu osadzania prekursora węglowego pozwala na uzyskanie warstewek o większej grubości. W badanym kompozycie zaobserwowano, w zaleŜności od wielkości i połoŜenia sfer, powłoki węglowe o grubości od 1 do 5 µm. Cieńsze warstewki wytworzono w miejscach, do których dostęp płynnego prekursora był ograniczony, np. przez zbyt małe lub częściowo zamknięte pory w sferach Al2O3. Proces pirolizy prekursora wywiera równieŜ wpływ na właściwości tribologiczne wytworzonego węgła szklistego. Temperatura i czas karbonizacji, z reguły, wpływają na zwiększenie wytrzymałości i twardości węgla szklistego. Infiltracja ciekłym stopem osnowy pokrytych węglem szklistym preform ceramicznych wywiera wpływ na właściwości wytrzymałościowe kompozytu. Za niskie ciśnienie i za mała płynność stopu mogą spowodować, Ŝe nie wszystkie sfery zostaną wypełnione całkowicie, a powstałe pustki zmniejszą wytrzymałość. Porównawcze badania tribologiczne kompozytu z osnową ze stopu AC-AlCu3Mg1, zawierającego 10% Al2O3 oraz kompozytu hybrydowego, ze sferami Al2O3 pokrytymi węglem szklistym, we współpracy z Ŝeliwem GJL-300 w warunkach tarcia technicznie suchego wykazały dobry wpływ węgla na współczynnik tarcia i zuŜycie. Współczynnik tarcia przy prędkości v = 2,5 m/s i nacisku jednostkowym p = 2 MPa po dotarciu skojarzenia wynosił 0,08÷0,12 dla kompozytu z węglem szklistym i 0,25÷0,32 dla kompozytu zawierającego tylko ceramiczne sfery. Słowa kluczowe: kompozyty hybrydowe, struktura, tlenek glinu, węgiel szklisty, właściwości tribologiczne, smar stały The influence of hybrid composites structure on their tribological properties 19 INTRODUCTION The structure of engineering materials is one of the most essential factors which modify their functional properties. Their tribological properties such as friction coefficient and resistance to sliding wear determine the kind of material to be used for the design of sliding parts in machines. Therefore, the proper selection of materials for sliding pairs seems absolutely fundamental. This selection should be focused on the chemical composition as well as the structure. From the theoretical point of view, the magnitude of friction forces depends on the shear strength of one of the component materials or on their structure, hardness and sliding surface topography. To reduce friction forces, a material having a possibly low shear strength, high hardness and low roughness should be selected. It is not easy though to find solid materials which would meet these requirements. Therefore, manufactured hybrid composite materials are composed of a matrix and two kinds of discrete phases. One of them increases the hardness, whereas the other one decreases the shear strength. These principles constituted the basis for the investigation project [1], carried out at the Silesian University of Technology, on a hybrid composite containing two reinforcing phases i.e. aluminum oxide which increases the strength properties (compressive strength and hardness) and glassy carbon which mitigates the friction. The additional function of porous aluminum oxide spheres and glassy carbon layers is to reduce the composite density. Glassy carbon has a density of 1420÷ ÷1540 kg/m3. The manufacturing technology of ceramics, porous pre-forms used for the production of the composite has been described in [2-4] while that of the composite itself in [5, 6]. The present paper discusses the effect of the structure of the hybrid composite containing ceramic spheres and thin films of glassy carbon as the reinforcing phase on the tribological properties in sliding contact with gray cast iron. SELECTION OF STRUCTURE COMPONENTS FOR SLIDING COMPOSITES From the tribological point of view, the basic criterion for designing hybrid composites is the friction hypothesis elaborated by Ernst and Merchant [7], which helps to calculate the friction coefficient. According to this hypothesis, the friction coefficient in sliding contact can be calculated from the following equation: µ= τ H + tgα (1) where: τ - the mean shear strength of the adhesion junction in the contact zone [MPa], usually the shear strength of the weaker material (shearing takes place only inside glassy carbon layers, shear strength: τ = 30 MPa); H - the hardness of the hardest material in the pairing (ceramic spheres) MPa; α - the mean angle of inclination of real contact areas to the direction of the tangent force, equal to the angle of inclination of the roughness peaks (the cast iron surface is worn-in, with very low roughness). The tribological properties of a hybrid composite are conditioned by, inter alia, the number of phases and stereological features of each phase. The amount of glassy carbon, stereological features of the particles and the method of its pyrolysis determine the shear strength, and consequently the friction forces. The shear strength depends upon the temperature and time of pyrolysis. The amount of ceramic material, its stereological features and the distribution method in the matrix material determine the strength properties such as hardness and wear intensity of the tribological partner e.g. cast iron. A larger amount of oxide in the form of irregular particles with sharp edges intensifies the wear. The optimum amount of aluminum oxide ranges from 10 to 20%. The least wear intensity of cast iron at sliding contact is guaranteed by composites with aluminum oxide in the form of fibers or spheres. The latest solution which reduces the wear intensity of a sliding partner is a composite which contains ceramic foams made of porous spheres e.g. aluminum oxide [2, 3, 8]. The lower hardness of porous spheres in comparison with fully dense particles reduces the wear of cast iron but at the same time gives rise to some failures in the composites like wall crushing. Fragments of aluminum oxide might locally intensify the wear, however, coating their surfaces with continuous glassy carbon film mitigates the negative results of crushing. INFLUENCE OF CERAMICS UPON SLIDING PROPERTIES OF COMPOSITES In composites containing irregular Al2O3 particles manufactured up to the present, the oxide was introduced into the matrix after proper preparation. The distribution of the Al2O3 particles was closely dependent on their preparation and matrix stirring at the introduction of the particles, as well as upon the casting conditions. In the proposed technology, a pre-form with porous Al2O3 microspheres is produced first. The preform is obtained by means of gelcasting of a suspension of an α-Al2O3 powder (Alcoa CT 3000 SG) followed by high temperature sintering. In the ceramic skeletons, the microspheres merge (Fig. 2b) and interpenetrate in such a way that continuity of the pre-form is ensured and open porosity is generated. The spaces between the spheres can be filled with Al2O3 (concentrated polycrystalline phase) or air. The first option significantly increases the preform strength, whereas the other option makes it weaker. The diameters of the microspheres range between 200 and 1000 µm, with a mean value of 400 µm. In single spheres, holes of 40÷200 µm in diameter can be observed [8]. Such a structure of microspheres in the pre-form makes it possible to fill Composites Theory and Practice 14: 1 (2014) All rights reserved 20 A. Posmyk, J. Myalski them with liquid substances i.e. a glassy carbon precursor and composite matrix alloy. The dimensions of the microspheres and holes in their walls can be altered with the parameters of the production process. Spheres of larger diameters facilitate the infiltration process with metal. However, when the matrix is filled with metal, areas with a surface close in size to that of an inner cross-section of a sphere which contain nothing but the matrix alloy are formed in the composite. This might mean weaker sliding properties due to the possible occurrence of adhesive tacking with a sliding partner. Smaller diameters of microspheres cause an increase in their number, thickness reduction of their walls and contraction of the area filled exclusively with the matrix alloy. Uniform distribution of ceramics over the friction surface will prevent the tendency to adhesion and reduce local friction forces inside the spheres filled with the matrix metal. The pre-form can feature diverse porosity. From the tribological point of view, the Al2O3 content should range between 10 and 20% i.e. the porosity of the ceramic pre-form should be 80÷90%. INFLUENCE OF GLASSY CARBON ON SLIDING PROPERTIES OF COMPOSITES Composites manufactured in recent years have contained glassy carbon introduced into the matrix, after a) prior preparation, in the form of irregular particles [5]. Uniform distribution of the carbon particles depended upon the kind of applied preparation and the conditions of their introduction into the liquid metal by stirring. The conditions of composite casting in a mould were also very important. In spite of the fact that a homogeneous composite suspension is obtained, the transfer of particles may occur during crystallization caused either by a crystallization front or sedimentation due to the different specific gravities of the carbon particles and matrix alloy (Fig 1a). In consequence, a greater concentration of particles is observed upon the outer surface or inside the cast. In practice, it is not possible to obtain a specific composite product with uniformly distributed carbon particles using casting methods. In the case of the composite under investigation, a liquid carbon precursor is introduced into a ceramic foam and not into the matrix. Then pyrolysis of the precursor is performed [1]. The method enables uniform distribution of glassy carbon over the walls of the ceramic spheres (Figs. 1b, 2b and 3) and eliminates stirring or any hazards of sedimentation or conglomeration present in composite casting with glassy carbon particles. As a result, the composite features better tribological properties since places deprived of glassy carbon functioning as a solid lubricant are reduced to a minimum. b) Fig. 1. Structure micrograph of composite produced using stirring (a) and infiltration of ceramic pre-form with glassy carbon precursor (b): 1- Al2O3, 2 - matrix alloy, 3 - phase precipitations, 4 - glassy carbon/particles layer Rys. 1. Mikrofotografia struktury kompozytu z węglem szklistym wytworzonego metodą mieszania (a) i przez nasączanie ceramicznej preformy prekursorem węgla szklistego (b): 1 - Al2O3, 2 - stop osnowy, 3 - wydzielenia fazowe, 4 - cząstki/warstewka węgla szklistego a) b) Fig. 2. Structure micrograph of composite after infiltration with matrix alloy (a) and joint of three ceramic spheres (1 in Fig. b) coated with layer of glassy carbon and filled with matrix alloy Rys. 2. Mikrofotografia struktury kompozytu po infiltracji stopem osnowy (a) i połączenia trzech sfer ceramicznych (1 na rys. b) pokrytych warstewką węgla szklistego (4) i wypełnionych stopem osnowy (2) Composites Theory and Practice 14: 1 (2014) All rights reserved The influence of hybrid composites structure on their tribological properties a) 21 b) Fig. 3. Micrographs of border zone between glassy carbon coated ceramic sphere wall and matrix alloy (a) and sphere filled with matrix alloy, partially coated with glassy carbon (b) Rys. 3. Mikrofotografie granicy pomiędzy pokrytą węglem szklistym ścianką ceramicznej sfery i wypełnieniem stopem osnowy (a) oraz sfera zapełniona stopem osnowy (b) pokryta częściowo węglem szklistym The wear conditions are mitigated and local adhesion of the sliding surfaces is prevented. Moreover, the production costs of machine parts are lower. Stirring is not required thus casting tools and stirrers are not worn down constantly by a stream of matrix alloy with sharp edged ceramic particles. The thermal properties of glassy carbon such as thermal conductivity λ ranges from 1.59 to 6.3 W/(K·m) and the thermal expansion coefficient α = = 2.2x10–6 in 20÷100°C and 3.2 x10–6 at temperatures of 100÷1000°C improve the dimensional stability of the composite which allows the application of this composite in the production of heat engines e.g. combustion engines. Low shear strength (30÷50 MPa) and high hardness 230÷340 HV reduce the friction forces. A compressive strength of 480 MPa is sufficient for sliding pairings to operate under high compressions. Comparative tribological studies on a composite with an AC-AlCu3Mg1 alloy matrix containing 10% Al2O3 and the hybrid composite in which aluminum oxide spheres have been coated with glassy carbon sliding against GJL-300 cast iron in air, demonstrate the positive influence of glassy carbon upon the friction coefficient and wear of both the cast iron and the composite. The friction coefficient at the relative speed of 2.5 m/s and unit pressure of 2 MPa after contact wearing-in was 0.08÷0.12 for the composite with glassy carbon and 0.25÷0.32 for the composite with ceramic spheres exclusively. The application of aluminum or magnesium alloys as matrix materials lowers the composite density but worsens the tribological properties due to the tendency of the metals to form adhesive tacking with the majority of engineering materials. Therefore the best sliding properties could be achieved when precipitation hardened alloys (e.g. alloys for plastic processing) are used as a matrix. The precipitations of phases distributed inside the aluminum oxide spheres reduce the tacking tendency which in turn reduces the friction forces and wear. Figures 1b and 2a show the matrix alloy with precipitations inside the ceramic spheres before sliding and Figure 4 after sliding against cast iron. The matrix material should facilitate the formation of sliding film from the wear products of glassy carbon. As a result, sliding contact, e.g. cast iron-matrix alloy, would be replaced by cast iron-glassy carbon sliding contact. a) b) INFLUENCE OF MATRIX MATERIAL UPON SLIDING PROPERTIES OF COMPOSITES Pre-forms made of ceramic foam coated with glassy carbon are subjected to pressure infiltration with the selected matrix alloy. Aluminum or magnesium alloys can be used to produce low density composites. If the use of matrix material with an elevated melting point appears necessary, e.g. copper or silver, the process of infiltration will have to be carried out in a vacuum or under protective gas to prevent glassy carbon oxidation and deterioration of the sliding properties. Fig. 4. Micrograph of inside of ceramic sphere filled with hardened matrix alloy precipitations (a) and chemical analysis of precipitations (b) Rys. 4. Mikrofotografia wnętrza sfery ceramicznej wypełnionej stopem umacnianym wydzieleniowo (a) i analiza składu chemicznego wydzieleń (b) Composites Theory and Practice 14: 1 (2014) All rights reserved 22 A. Posmyk, J. Myalski The change of the composite colour after sliding is the evidence of good adhesion between the wear debris of the glassy carbon and the matrix material. Dark areas upon the surface after friction account for the deposition of a sliding film. Figure 4 shows micrographs of the composite surface after sliding contact with GJL-300 cast iron in air. a) b) Fig. 5. Surface view of composite after sliding against cast-iron GJL-350 in air (a) and border zone between sphere and matrix alloy with initial exposure of a sphere inside (b) Rys. 5. Widok powierzchni kompozytu po współpracy ślizgowej z Ŝeliwem GJL-350 w warunkach tarcia technicznie suchego (a) i granicy sfery i stopu osnowy z początkiem odsłonięcia wnętrza sfery (b) The exposure of aluminum oxide spheres coated with glassy carbon film (darker circular areas) are visible upon the composite surface (Fig. 5a) together with a sliding film of glassy carbon and graphite from cast iron formed during friction. The lighter areas represent the places where the sliding film has been removed and the brightest areas represent the fragments of exposed ceramics. Figure 5b presents the junction of ceramic spheres filled with the matrix alloy with the deposited sliding film. The wear debris of glassy carbon and graphite from cast iron have been deposited at cross-sections of the ceramic walls as well. Exposure of the inside of the ceramic sphere took place as a result of wear followed by slight wear of the carbon film which coated the inner part of the sphere. CONCLUSION The structure of a hybrid composite containing porous ceramic spheres as the reinforcing phase and Composites Theory and Practice 14: 1 (2014) All rights reserved layers of glassy carbon functioning as a solid lubricant can be shaped in a three-stage manufacturing process consisting of the production of a foamy preform by the gelcasting method, saturation with the carbon precursor followed by precursor pyrolysis and infiltration with the matrix alloy. The first stage enables one to obtain the required porosity of a pre-form which determines the amount of ceramics in the composite and stereological features of the spheres such as dimensions of the pores or wall thickness. The second stage opens the possibility to control the shear strength and hardness of glassy carbon with the amount of carbon precursor introduced and the process parameters. By selecting a matrix alloy with hard precipitations and parameters of infiltration, it is feasible to control the tendency of the matrix material to adhesive tacking. The tribological properties in the final composite constitute the operational superposition on all the manufacturing stages. The structure and tribological properties of the presented composite have been obtained under the established conditions based on theoretical analysis and literature available as well as the authors’ professional experience. However, further multifactor optimization studies which will determine the best composite structure for tribological purposes are required. Acknowledgements Financial support of Structural Funds in the Operational Programme - Innovative Economy (IE OP) financed from the European Regional Development Fund - Project No POIG.0101.02-00-015/08 is gratefully acknowledged. REFERENCES [1] Method for production of aluminium-ceramic composite including solid lubricants, Patent application P. 398311 [WIPO ST 10/C PL398311] 2012. [2] Santacruz I., Moreno R., Preparation of cordierite materials with tailored porosity by gelcasting with polysaccharides, International Journal of Applied Ceramic Tech. 2008, 5, 74-83. [3] Potoczek M., Gelcasting of alumina foams using agarose solutions, Ceram. International 2008, 34, 661-667. [4] Bednarek P., Szafran M., Sakka Y., Mizerski T., Gelcasting of alumina with a new monomer synthesized from glucose, Journal of European Ceramic Society 2010, 30, 1795-1801. 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