Microsoft Word - numero 14 articolo 6 V. 52 In di V. Un v.d L. Un AB pro gal yea flu (e.g In wa coa ben mi KE IN In beh Zn at cha Fou dif (17 7.0 cha pos duc P Di Cocco et alii, nfluence ip galva Di Cocco niversità di Ca dicocco@unicas Zortea niversità di Ro BSTRACT. In otection tech lvanizing is ars: some ch uidizing prop g. … Pb!). this work, t as investigate ated ipersan nded specim cromechani EYWORDS. H NTRODUCTIO rinciples Actually corrosiv the last dec haviour” orie n-based coatin high tempera aracterized by ur intermetal fferent Fe con 7-28 wt %), a 0 and 11.5 w aracterized by ssible to obt ctile behaviou P Frattura ed Inte e of dipp anized c o assino, Di.M.S s.it oma “Sapienza n the last ye hniques, int a classical p hemical elem perties, some the influence ed consideri ndelin steel mens were sms were id Hot dip galva ON s of hot dip g , it is still one e environmen cades, new nted to use in ngs growth is ature [5]. Ma y different ch llic layers are ntents (Fig. 1) and by a very wt%, with H y a radial orie ain a  phas ur and by a ve tegrità Strutturale ping tim coatings S.A.T., via G a”, Dip.I.C.M ears, the att troducing in process aime ments are ad etimes repla e of dipping ing differen specimens observed entified as lo anizing; Inte galvanizing h e of most im nts [1]. investigation n high plastic a diffusion d any intermeta hemical comp e usually ob ). The inner l low thicknes HCP unit cell ented morpho se with not-o ery low Fe co e, 14 (2010) 52 me on c s with S G. Di Biasio, 4 M.A., Via Eu ention to en nnovative wa ed to genera dded in the ced by Sn) b time and co t Sn and Ti were invest by means ongitudinal a ermetallic ph have remaine mportant proc s on bath c deformation driving pheno allic phases c ositions, mor served in cla layer, namely ss, often negl l and a brittl ology, due to oriented morp ontent. -63; DOI: 10.322 cracking Sn and T 43 03043, Ca udossiana 18, nvironmenta ay oriented te coatings bath with but sometim oatings chem i contents. M tigated by m of a LO and radial cr hases; Dama d unchanged cessing techni compositions ns [1-4] or in r omenon, whe ould be obta rphologies an assical Zn, Z  phase (gen ligible [3].  p le behaviour. growth mech phology [6]. 1/IGF-ESIS.14.06 g during Ti conte Cassino (FR), I Roma, Italy al topics led to optimize on iron-base different aim mes these ele mical compo Main damag means of be OM (Light racks. age analysis. d since this c ique to prote s were perfo reinforced co ere Zn and Fe ained depend nd mechanical Zn-Pb and Z nerally BCC), phase is chara .  phase, lo hanisms. Dep The outer la 6 g bendin ents Italy d a new app e different c ed surfaces, ms (e.g., Pb ments are d ositions on d ging microm ending tests Optical M oating came ct carbon ste ormed to ge omponents. e atoms are c ding on Zn c l behaviour. Zn-Sn coating is characteriz acterized by a ocated betwee pending on th ayer (η phase ng of ho proach solut coating prop used uncha b is really im dangerous fo damaging mi mechanisms s. Longitudi Microscope): into use ove eels against co enerate coatin characterized contents [3]: gs: they are zed by the hi a Fe content en  and the he hot dipping e, HCP) is ch ot tion in class perties. Hot- anged since mportant for or human he cromechani in hot dip z inal sections main dam er 200 years orrosion in m ngs “mechan by interdiffu these phases characterized ighest Fe con ranging betw e outer phase g conditions, haracterized b sical -dip 200 r its ealth sms zinc s of mage ago. many nical sion s are d by ntent ween e, is it is by a http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true mailto: v.dicocco@unicas.it In inv obs MA Th aqu g/l dip T this work, th vestigated con servations. ATERIAL AN hree dif were pe fifteen c he following p ueous solutio l ZnCl2 and 2 pped in the zin Figure 2: D T he influence nsidering diff ND EXPERIM fferent bath c rformed at 4 coating, 3 mm procedure wa n 20% H2SO 220 g/l NH4 nc bath. All g C 0.090 Different clam of dipping t ferent Sn and Fig MENTAL PRO compositions 60°C ± 2 °C m thick comm as used for co O4 at 50°C for 4Cl at environ galvanized pla Si 0.167 T (a) mping configura V. Di Cocco et time and coa d Ti contents gure 1: Zn coat OCEDURES s were consid C, considering mercial ipersan oating the pla r 10 minutes, nment tempe ates were air c Mn 0.540 Table 1: Steel c ations: a) Starti t alii, Frattura ed atings chemic s by means o ting section: in dered: pure Z g five differen ndelin carbon ates. They we washed in fre erature for 2 cooled. P 0.010 chemical comp (b) ing position; b d Integrità Strutt cal composit of bending te ntermetallic pha Zn, Zn + 3 % nt dipping tim n steel plates w ere degreased esh water, flu minutes and S 0.004 position (wt % b) Pure applied turale, 14 (2010) tions on dam ests and LOM ases. %wt Sn, Zn mes: 15, 60, 1 were used (Ta and rinsed w uxed in an aqu d dried for 10 Al 0.051 %). (c) bending mom ) 52-63; DOI: 10 maging microm M (Light Opt + 0.5 %wt T 180, 360 and ab. 1). with alcohol a ueous solutio 0 minutes at Fe Bal. ment; c) 30° po 0.3221/IGF-ESIS. mechanisms tical Microsco Ti. Zinc coat 900 s. For all and pickled in on containing 100°C and t sition [8,9]. 14.06 53 was ope) tings l the n an 280 then http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true V. 54 Mic per (0.1 Ben inv equ dam me def EX Int obt one mic imp usi dif add F Di Cocco et alii, crostructure rforming scan 1 N – 15 s). nding tests w vestigated con ual to 35 mm maging mech etallographica fined as crack XPERIMENT termetallic pha ig. 3 sho intermet eutectic tain “multilay e higher than crostructure, plies an evide ng pure Zn fferent growth dition implies F Frattura ed Inte analysis was nning electro were perform ndition. An e m, that corre hanisms for ally prepared ks number/co TAL RESULTS ases growth kin ows binary Zn tallic phases a transformatio yer” coatings n the Sn con but only flui ent influence baths are ch h kinetic, wi s a decrease fo Figure 4: 300 500 700 900 1100 1300 1500 1700 Te m p e ra tu re  [° C ] 0 100 200 300 400 Th ic kn e ss  [ m ] tegrità Strutturale s performed on microscop med by means electromecha esponds to a each investig and observed oating length S netics n-Fe and Zn and the secon on correspon with the “cla ntents used in idifies the ba on the phase haracterized b ith linear beh or the import Fi Coatings and 0 10 20 30 4 (Fe)f ( Fe ) (Fe)p 0 200 40 T    e, 14 (2010) 52 by means o pe (SEM) ana s of a non-st anical 100kN a bending an gated loading d by means o [12-14]. n-Sn phase dia nd does not s nding to very assical” interm n industrial a ath. Focusing e thickness-tim by a parabolic haviour in w tance of ζ pha (a) igure 3: Phase (a) intermetallic p 40 50 60 70 80 Zn [wt%]    L+  L 00 600 800 Time [s]  Coating -63; DOI: 10.322 of traditional alysis, with E tandard devic testing mac gle equal to g condition, of a LOM. D agrams. The show interme high Sn cont metallic phase applications, i g the interme me curves, es c diffusion c which growth ase with respe diagrams. (a) Z phases kinetics 90 100     ()→ 150 200 250 300 350 400 450 Te m p e ra tu re  [° C ] 1000 10 20 30 40 Th ic kn e ss  [ m ] 1/IGF-ESIS.14.06 l metallograp EDS. Vickers ce (Fig. 2a) a chine was use 30° (Fig. 2c longitudinal Damage level w first is chara etallic phases tents. Both pu es. Considerin it implies tha etallic growth specially cons controlled gro is interface ect to the oth Zn-Fe; (b) Zn- . (a) Zn bath; ( 0 10 20 30 40 0 00 00 00 00 0 200   6 phic techniqu microhardne and repeated ed, consideri c) [7-11]. Fin sections of was evaluated cterized by th and is charac ure Zn and Z ng that a cont at Sn additio h kinetics (Fig sidering η and owth (Fig. 4a controlled [ her intermetal (b) Sn. (b) (b) Zn + 3 %w 0 50 60 70 80 Sn [wt%] L 400 600 8 Time [s]  Coating ues (LOM ob ess tests were at least thre ing a crosshe nally, in orde the bended d in term of he presence o cterized by th Zn + 3 %wt S tent of 3% of n do not mo g. 4), investig d ζ phases. C a). The Sn ad [2], Fig. 4b. F llic phases (Fi wt Sn bath. 90 100 (βSn)→ 00 1000 bservations) e also perform e times for e ead displacem r to identify specimens w “cracks dens of the “classi he presence o Sn baths allow f Sn is a facto odify the coa gated Sn con Coatings obtai ddition impli Furthermore, ig. 4a and 4b) and med each ment the were ity”, ical” of an w to or of ating ntent ined ies a , Sn ). http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true Ti ma Fur %w con Co pro pre com (ab che neg Mic Fo additions im any new inte rthermore, so wt Ti, no Znx nsequent Ti a oating micros obably observ esent near iro mpact phase bout 7.6% an emical comp gligible Ti and crohardness a cusing dark g mply a strong ermetallic ph olidification te xTiy intermeta and Zn air ox tructure is st ved, but the t on-coating in (Fig. 6b, dark nd 3.5%, resp osition analy d Fe content analysis show grey phase, its modification hases nucleat emperature s allic phases w idation, surfa trongly affec thickness is to nterface. The k grey), with pectively). Fur ysis show tha (1.6 %wt and ws an evident s microhardne (a) Figure 6: Z “like δ”, d 0 200 400 600 800 1000 1200 1400 1600 1800 0 Te m p e ra tu re  [° C ] V. Di Cocco et n of coatings te and grow trongly increa were observed ace colours ra Figure 5: Z ted by the T oo low to be outer layer i a sort of “ch rthermore, a at the light g d 0.6 %wt, re increase of V ess is up to tw Zn-Ti coating m dark grey phase 0 10 20 ? Zn 2 Ti Zn 3 Ti Zn 5 Ti Zn 1 0 Ti Zn 1 5 Ti ? t alii, Frattura ed microstructu w with differ ases also for l d [16], due to ange from gre Zn-Ti phase di Ti addition (F described an is characteriz hain” morpho lamellar stru grey phase is spectively). Vickers values wo times high microstructure e, light grey pha 30 40 50 Ti [wt% ? ? Zn Ti d Integrità Strutt ures. Conside rent chemica low Ti additio the low Ti c ey to violet. iagram [15]. Fig. 6). Near d quantified u zed by a mor ology, that is ucture is obse almost pure s with the incr her than the i (different mag ase and lamella 60 70 80 %] ? Zn Ti 2 turale, 14 (2010) ering binary Z al compositio ons. Consider content. Due r the iron su using a LOM re complex m characterized erved mixed e Zn, and lam rease of the F ron substrate (b) gnifications): ar structure. 0 90 100 αTi↔βTi ) 52-63; DOI: 10 Zn-Ti phase ons, from Z ring the inves to the Ti add ubstrate, a so M. A compact microstructure d by high Fe with a light g mellar structu Fe and Ti con e. 0.3221/IGF-ESIS. diagram (Fig Zn15Ti to Zn stigated Zn + dition, and to rt of  phas “like " pha e. It is evide e and Ti cont grey phase. E ure shows a ntents (Tab. 2 14.06 55 g. 5), nTi2. + 0.5 o the se is se is nt a tents EDS not 2). http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true V. 56 Di Cocco et alii, Ele T F Z Tot Frattura ed Inte ement Ti Fe Zn tal D tegrità Strutturale Weight % 3.48 7.62 88.90 100.00 Dark grey pha Ele T F Z To Figure 7: Zn e, 14 (2010) 52 Atom % 4.63 8.70 86.68 100.00 ase ement Ti Fe Zn tal La n + 0.5 %wt T -63; DOI: 10.322 Elem Ti Fe Zn Tota Weight % 1.62 0.60 97.78 100.00 amellar struct i bath. SEM-E 1/IGF-ESIS.14.06 ment i e n tal Li Atom % 2.20 0.70 97.10 100.00 ture EDS coating su 6 Weight % 0.17 0.17 99.66 100.00 ight grey pha urface analysis Atom % 0.23 0.20 99.57 100.00 ase http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true Ti tim lam Co Ben mic 3 % the cha val Da (co Co dis to pro ana cor Co inc ana inte is n strongly influ mes higher if c mellar structur Figure 8 atings mechan nding mome crostructure o %wt Sn bath: e investigated aracterized by lue with the b amage analysi onsidering gra onsidering co tribution foll the  phase: opagation co alogous dama rresponding t onsidering cra crease of the alytical relatio ermetallic ph not a frequen Table uences interm compared to re + light gre 8: Zn – 0.5 %w nical resistance ent – bendin on coatings m higher “YS” bending ang y lowest “YS bending angle is shows an e ains shapes, d atings obtain ows the “clas these cracks uld be arrest age morpholo to higher dipp acks density intermetallic onship betwee ases thicknes t phenomeno e 2: Zn + 0.5 % metallic phases the coating o y phase) thick wt Ti bath. Dip and damage m ng angle dia mechanical re ” values are ob gles. The wors ” values: furt e is observed. evident influe distribution an ned using a Z ssical” morph could either ted either in ogy. Focusing ping times. as a quantita c phases dam en dipping tim ss. However, on. Th ic kn e ss  [  m ] V. Di Cocco et %wt Ti bath. I s growth kine obtained with kness is up to pping time influ micromechanis agrams (Fig. esistance: the btained and t st behaviour c thermore, esp nce of the co nd dimension Zn bath (Fig hology (Fig. 1 be arrested c n  phase or g the specime ative damage mage, for all me and dama considering b 0 100 200 300 400 500 600 0 20   t alii, Frattura ed “Like δ” phase 181 ntermetallic ph etics (Fig. 8): a h a Zn or Zn o the 95% of uence on the c sms 9) show t best behavio the coated pla corresponds t pecially for lo oating chemic ns) (Fig. 10, 11 g. 10) and fo ). Lower dipp corresponding r at inte en compressi e parameter, the investiga age level, due both Fig. 13a 00 400 6 Time [s Outer layer d Integrità Strutt Compact dark grey phase 302 hases microhar after 180 s, co + Sn baths. “ the global co coating and inte the influence our correspon ates are chara to the coating ower dipping cal compositi 1 and 12). ocusing the te ping times im g -interfac erface. Highe ion side, only the increase ated dipping to the strong a and 13b, it i 600 800 1 s] Coating turale, 14 (2010) Lamellar structure 66 rdness values[H oating thickn “Mixed” zone oating thickne ermetallic phas e of coating nds to the co acterized by h g obtained us times, a decr ion, microstru ensile specim mply radial cra ce or propaga er dipping ti y some therm e of the bend times. It wa g influence of is evident tha 1000 ) 52-63; DOI: 10 Light grey phase 35 HV0.1]. ness with Ti is e (compact d ess (180 s). ses thickness e g chemical c oatings obtain higher resistan sing a Zn + 0 rease of the b ucture and ph men side, inte acks nucleatio ate in  phase imes are cha mal cracks we ding angle al as not possib f the dipping at cracks arres 0.3221/IGF-ESIS. s more than th dark grey phas evolution. composition ned using a Z nce values fo .5 Ti bath, th bending mom hase morpho ermetallic ph on correspond e. In this case aracterized by re observed o lways implies ble to identify conditions to st at -inter 14.06 57 hree se + and Zn + or all hat is ment logy hases ding e the y an only s an y an o the rface http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true V. 58 Fig Co pha dis low cor Di Cocco et alii, gure 9: Dippin onsidering coa ases distribut tribution is n wer dipping t rresponding  Frattura ed Inte ng time influenc atings obtaine tion always f not different i times imply r -interface tegrità Strutturale ce on half angl ed using a Zn follows the “ f compared t radial cracks or propagate e, 14 (2010) 52 le-bending mo n + 3 %wt Sn “classical” mo to the damage nucleation co in  phase. I -63; DOI: 10.322 oment curve: a) n bath (Fig. 1 orphology (F e distribution orresponding In this case th 1/IGF-ESIS.14.06 ) Zn bath; b) Z 11) and focus Fig. 1). From n formerly des g to the  ph he propagatio 6 Zn + 3 %wt Sn sing the tensil m a morpholo scribed (coati hase: these cr on could be a (a) (b) (c) n bath; c) Zn + le specimen s ogical point o ing obtained u racks could e arrested either + 0.5 %wt Ti b side, intermet of view, dam using a Zn ba either be arre r in  phase o bath. tallic mage ath): ested or at http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true  com interface. mpression sid Time 15 60 18 36 90 Figure 10: Higher dipp de, no therma e [s] 5 0 80 60 00 : Coatings obta ing times are al cracks were T ained using a Z V. Di Cocco et e characteriz e observed, al Tensile side Zn bath: LOM t alii, Frattura ed ed by an an lso correspon M intermetallic p d Integrità Strutt alogous dam nding to highe phases damage turale, 14 (2010) mage morpho er dipping tim Compressi e morphology a ) 52-63; DOI: 10 logy. Focusin mes. ion side at 30° half ben 0.3221/IGF-ESIS. ng the specim nding angle. 14.06 59 men http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true V. 60 Di Cocco et alii, Time 15 60 18 36 90 Frattura ed Inte e [s] 5 0 80 60 00 Figure tegrità Strutturale T 11: Coatings o da e, 14 (2010) 52 Tensile side obtained using amage morpho -63; DOI: 10.322 g a Zn + 3 %w ology at 30° ha 1/IGF-ESIS.14.06 wt Sn bath: LOM alf bending ang 6 Compressio M intermetallic gle. on side c phases http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true Time 15 60 18 36 90 e [s] 5 0 80 60 00 L T Figure 1 LOM intermet V. Di Cocco et Tensile side 2: Coatings ob tallic phases da t alii, Frattura ed btained using a amage morpho d Integrità Strutt a Zn + 0.5 %w logy at 30° hal turale, 14 (2010) Compressi wt Ti bath: lf bending angl ) 52-63; DOI: 10 ion side le. 0.3221/IGF-ESIS. 14.06 61 http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true V. 62 Di Cocco et alii, Fig Frattura ed Inte Figure 13: gure 14: Coatin Figur tegrità Strutturale (a) Coatings obta (a) ngs obtained u (a) re 15: Coatings (a) “ e, 14 (2010) 52 ained using a Z using a Zn + 3 s obtained usin like ” phase; -63; DOI: 10.322 Zn bath. Dama %wt Sn bath. ng a Zn + 0.5 % (b) outer layer 1/IGF-ESIS.14.06 age evolution in Damage evolu %wt Ti bath. D (only radial cr 6 (b n: (a)  phase; (b ution in: (a)  p (b Damage evolut racks). b) (b)  phase. b) phase; (b)  ph b) tion in: hase. http://www.gruppofrattura.it http://dx.medra.org/10.3221/IGF-ESIS.14.06&auth=true Cra arr Co dis a) b) c) Fo gra Cra Zn sho dar res CO On    RE [1] [2] [3] [4] [5] [6] [7] [8] [9] [10 [11 [12 [13 [14 [15 [16 I acks density i est at -inte onsidering coa tribution (Fig Radial crack Longitudina Light grey p cusing the sp ains were obse acks density v n and Zn + 3 ow any radial rk grey grains istance. ONCLUSION n this work investigated Microscop n the basis of Sn addition diffusion ph phases chara Coatings w investigated Both Zn an addition im lamellar stru EFERENCES ASTM Han A.R. Marde Y. De Abre 682. T. Evangelo G. Voct, J.B V. Di Cocco J.L. Duncan J.L. Duncan S. Natali, V 0] S. Natali, F. 1] R. de Kort, 2] S.R. Kim, J. 3] S.R. Kim, J. 4] E.A. Sacco, 5] T.B. Massal 6] A.R.B. Verm I is lower if co erface is a mo atings obtaine g. 6). Focusin ks in “like ” al cracks at st phase grains d pecimen comp erved. Furthe values in “lik %wt Sn bath or longitudin s debonding ( NS k, the influen d considerin e) observatio the experime to the Zn ba henomena. T acterized by d with Sn additi d conditions. O nd Zn+Sn co mplies a new ucture + light S ndbook Corro er, Progress in eu, A. Da Silv os, G. Papadi B. Reumont, A o, F. Iacoviel n, S.-C. Ding, n, S.-C. Ding, V. Di Cocco, F . Iacoviello, V W. Kets, H. .A. Narin, En .A. Narin, En , N.B. Alvarez lski, Binary al ma, W.J. van ompared to c ore frequent p ed using a Zn ng the tensile s phase; teel – “like ” debonding, es pression side, ermore, longi ke ” phase ar hs (Fig. 15). T nal cracks (Fig (Fig. 12). Thi nce of dippin ng different ons. ental results, t ath influences Ti addition str different Fe a ion are char On the contra oatings are ch damaging m t grey phase), osion, Hot dip n Materials Sc va, A. Ruiz, R imitrou, Surfa A. Iost, J. Fo llo, S. Natali, , W.L. Jiang, I , W.L. Jiang, I F. Iacoviello, V. Di Cocco, van Kempen ngineering Fra ngineering Fra z, J.D. Culcas lloy phase dia Ooij, Surface V. Di Cocco et coatings obtai phenomenon n + 0.5 %wt T specimen side ” phase interfa specially corre , both longitu tudinal crack re analogous The outer laye g. 15b): this l is damaging m ng time and c Sn and Ti the following s the intermet rongly modif and Ti conten racterized by ary, Ti additio haracterized micromechanim probably due p coatings (19 cience, 45 (20 R. Réquiz, N. A ace and Coati ct, Surface an In: Internatio International International La Metallurgi In: 32° Conv n, Surface Scie acture Mecha acture Mecha si, C.I. Elsner agrams, Vol. 2 e & Coatings t alii, Frattura ed ined using Z n (Fig. 14a and Ti bath (Fig. e, three differ face or in “like esponding to udinal cracks s were also ob to the values er (dark grey layer is charac mechanism is oatings chem contents by g conclusions tallic phases t fy coating mi nts. an increase on implies a s by the prese ms: microvoi e to dark grey 999) 13. 000) 191. Angulo, R. A ings Technolo nd Coatings T onal Conferen Journal of M Journal of M ia Italiana 7-8 vegno Nazion ence, (2001) 4 anics, 65 (200 anics, 65 (200 r, A.R. Sarli, S 2, ASM, Meta Technology, d Integrità Strutt n baths, for d 14b). 12), phases d rent damage m e ” phase gr higher bendi at steel – “lik bserved at “li s observed in phase + lame cterized by th s the respons mical composi means of b could be sum thickness evo crostructure. of the spec strong decrea ence of crack ids are evide y grains debo Alanis, Surface ogy, 145 (200 Technology, 1 nce on Crack Mechanical Sci Mechanical Sci 8 (2004) 49. nale AIM, Fer 495. 00) 573. 00) 595. Surface & Co als Park, Ohio 89 (1997) 13 turale, 14 (2010) all the invest distribution is morphologies rains ing angles. ke ” phase in ike ” phase g n  phase laye ellar structure he presence o ible of the ev itions on dam bending test mmarized: lution, proba A new oute cimens mech ase of the mec ks as main da ent in the ou nding. e and Coating 01) 176. 139 (2001) 26 Paths, Parma iences 41 (19 iences, 41 (19 rrara, Italy, (2 oatings Techn o 44073 (1986 32. ) 52-63; DOI: 10 tigated condit really far fro s were observ nterface and grains – outer ers in coating e + light grey f microvoids, vident decrea maging micro ts and LOM ably due to Sn r layer appea hanical resista chanical resis amaging micr uter layer (da gs Technolog 65. a, Italy (2006) 99) 249. 999) 261. 2008) 39. nology, 168 (2 6) 0.3221/IGF-ESIS. tions, and cra om the “classi ved: in “like ” ph r layer interfa gs obtained u y phase) does , probably du ase of the coa omechanisms M (Light Op n influence to ars with diffe ance, for all tance. romechanism ark grey phas gy, 120-121(19 ) 12. 2003) 115. 14.06 63 acks ical” hase ace. using not ue to ating was ptical o the erent the m. 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