Abstract
Laser powder bed fusion (L-PBF) is an additive manufacturing technology that is gaining increasing interest in aerospace, automotive and biomedical applications due to the possibility of processing lightweight alloys such as AlSi10Mg and Ti6Al4V. Both these alloys have microstructures and mechanical properties that are strictly related to the type of heat treatment applied after the L-PBF process. The present review aimed to summarize the state of the art in terms of the microstructural morphology and consequent mechanical performance of these materials after different heat treatments. While optimization of the post-process heat treatment is key to obtaining excellent mechanical properties, the first requirement is to manufacture high quality and fully dense samples. Therefore, effects induced by the L-PBF process parameters and build platform temperatures were also summarized. In addition, effects induced by stress relief, annealing, solution, artificial and direct aging, hot isostatic pressing, and mixed heat treatments were reviewed for AlSi10Mg and Ti6AlV samples, highlighting variations in microstructure and corrosion resistance and consequent fracture mechanisms.
Highlights
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The aim of the present review is to summarize and discuss the effects induced by different HTs on the most studied alloys in the AM field: AlSi10Mg and Ti6Al4V
The effects induced by different heat treatments on as-built AlSi10Mg and Ti6Al4V samples produced via Laser powder bed fusion (L-powder bed fusion (PBF)) were reviewed
Summary
Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations. TTii66AAll44VV iinn ann α ++ ββ aallllooyy eexxhhiibbiitteedd pprroolloonnggeedd bbiiooccoommppaattiibbiillity,, hhiigghhfafattigiguueereres-isstiasntacnecaenadntdoutoguhgnhensse,sas,s awsewll ealsl haisghiegrhteernsteilnessilteresntgrethngatnhdadnedndsietyns(i4ty.41(4g.4/1cmg/3c,m[63],) [t6h]a)n tAhalSni1A0lMSig10aMllogya[l1lo7y,18[1].7,A18t]t.hAetsathmeestaimmee,timts ec,oirtrsocsoiornrorseiosinstraenscisetamnackeems iatkpeossistibploesstoibulese tionumseairninme arnidnecahnedmcichaelminicdaul sintrdieusstarnieds ianntdhienbthioembeiodmiceadl ificealdfifeoldr oforrthoorptheodpice,dcirca, ncrianl aianld aonrdthoordthoondtiocnimticpilmanptlsa[n1t9s–[2119]–.2A1].teAmtpemerpinegrintrgeatrtmeaetmntepnetrpfoermforemd eadt 4a0t04–0600–060◦0C°mCamkaeskeths e tThie6ATil64AVl4aVlloayllsouyitsaubitlaebfloerftohrethmeamnuafnaucftaucrtiunrginogf ocof lcdolednegningeinceocmopmopnoennetns t[s22[2].2]F.iFgiugruere1b 1sbhsohwoswas paoprotirotinonofotfhtheeTTi-i6-6AAl lpphhaasseeddiiaaggrraamm, where tthheerreeddisisoo-c-coonncceenntrtaratitoionnlinlienehihgihg-hlliigghhttsstthheeccoooolliinngg//hheaetaitnigngppatahthofoTf iT6iA6Al4lV4Valalollyo.y.InInththeesasmameefifigugurer,et,htheehhexeaxgaognoanlacllcolsoesded packed and the body cubic centered lattice structures of the α and β phases are illustrated, respectively. Starting from the β-region (T > TβTr = ~995 ◦C, [17]), where the Ti alloy shows a fully β-phase microstructure, to the room temperature, the β-phase is almost completely transformed into α-phase (~90 ÷ 95%) + β-phase (~5 ÷ 10%) due to the presence of Al and V alloying elements that stabilize the hexagonal closed packed α-phase and the body centered cubic β-phase, respectively [17,23].
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