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103

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105

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1000� h=}r= K]U QO xDiQopmW CWQO |rw] |=ylQD SEM Q}wYD "9 pmW"�O}U= QO Ca=U

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106

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|Q}oxH}Dv "45 l} QwirwU O}U= pwrLt QO xW}W h=}r= |=yxvwtv |Qwx]we u=tR V}=Ri= =@ "1GwQN p}rOx@ Qt= u}= xm O@=}|t Vy=m h=}r= |t=mLDU= X=wN '|vRw OYQO

"CU= xW}W Q=DN=U R= s}Urm w sw}v}twr; |=yuw}Ca=U 96 COt x@ xOWxOQwN h=}r= |=yxvwtvw sr=U h=}r= |=yxvwtv QO uwJ "2QO h=}r= Ov=tUB |rw] |=yVvD syU 'xDW=Ov OwHw |Y=N lQD xvwoI}yxW}W Mv QO I}B Q=t |=ylQD |Q}opmW x@ QHvt xm �� u; CN=U Ov}=Qi u}L

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�References� `@=vt1. Price, J.N. and Hull, D. \E�ect of matrix toughness on

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4. Megel, M.; Kumosa, L.; Ely, T.; Armentrout, D. and Ku-mosa, M. \Initiation of stress corrosion cracking in unidi-rectional glass/polymer composite materials", Compos-ites Science and Technology, 61, pp. 231-246 (2001).

5. Kumosa, L.; Armentrout, D. and Kumosa, M. \The ef-fect of sandblasting on the initiation of stress corrosioncracking in unidirectional E-glass/polymer compositesused in high voltage composite (non-ceramic) insula-tors", Composites Science and Technology, 62, pp. 1999-2015 (2002).

6. Metcalfe, A.G. and Schmitz, G.K. \Mechanisms of stresscorrosion in E-glass �laments", Glass Technology, 13,pp. 5-16 (1972).

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fracture of composite insulator GRP rods", IEEE Trans-actions on Power Delivery, 18, pp.684-693 (2003).

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107

A STUDY ON THE STRENGTHBEHAVIOR AND CRACKFORMATION MECHANISM INE-GLASS FIBER UNDERCORROSION CONDITIONSM. M. Shokrieh?shokrieh@iust.ac.irV. Nasirnasir@mecheng.iust.ac.irSchool of Mechanical EngineeringIran University of Science and Technology

Sharif Mechanical Engineering JournalVolume 28, Issue 3, Page 101-107, Research Note

c Sharif University of Technology

AbstractIn this study, the strength behavior and crack formationmechanisms of E-glass �ber exposed to a sulfuric acidenvironment for di�erent immersion times were investi-gated. In order to study strength degradation, E-glass�bers were immersed in sulfuric acid. The strength re-duction, sti�ness and fracture strain of �bers versus im-mersion times was studied. The corrosion mechanism ofE-glass �ber exposed to acid was examined by a quan-titative X-Ray Fluorescence (XRF) method. The re-sults showed that the corrosion of E-glass �ber was ac-companied by removal of Al, Ca and Fe ions from the�bers. Moreover, intact and degraded �bers were exam-ined by Scanning Electron Microscope (SEM) and En-ergy Dispersive x-ray Microanalysis (EDX) methods to

show the relation between the reaction of E-glass �berelements and the acid environment. The ion-depletion-depth model was used to study the fracture process. Theresults showed that by increasing the immersion timein acid, the spiral stress, induced due to the shrinkageof the E-glass �ber surface, caused axial cracks in the�bers. Di�erent points of the �bers in which cracks weregenerated were examined by the EDX method. The re-sults were used to explain the role of Al, Ca and Fe ionsin the creation of surface cracks on E-glass �bers sub-jected to sulfuric acid for di�erent immersion times. Byincreasing the immersion time of the glass �ber in sul-furic acid, the magnitude of strength of the glass �berwas reduced. Strength degradation was caused by de-pletion of Al and Ca ions of the glass �ber. Moreover,this degradation depends on �ber fabrication, type andconcentration of acid, and immersion time. After 192 hexposure time, based on the results of EDX, it could beseen that the depletion of Fe ions and their replacementwith the hydrogen of acid caused micro-crack initiationon the glass �ber surface, where Fe ions were leachedout. According to the ion-depletion-depth-model, byincreasing immersion time, the crack formation mech-anism was caused by the ion depletion of the E-glass�ber.

Key Words: glass �bers, stress corrosion, ion-depletion-depth model, crack, sulfuric acid.

? corresponding authorReceived 12 September 2010; received in revised form 24 May2011; accepted 25 July 2011.