Effect of Thermal Treatments Below Devitrification Temperature on the Magnetic and Magnetocaloric Properties in Mechanically Alloyed Fe70Zr30 Powders

Jou nal o Non-C ys alline Solids 609 (2023) 122267 A ailable online 14 Ma ch 2023 0022-3093/© 2023 The Au ho (s). Published by Else ie B.V. This is an open access a icle unde he CC BY-NC-ND license (h p://c ea i ecommons.o g/licenses/by- nc-nd/4.0/). E ec o he mal ea men s below de i i ica ion empe a u e on he magne ic and magne ocalo ic p ope ies in mechanically alloyed Fe 70 Z 30 powde s A.F. Manch´ on-Go d´ on a , * , J.S. Bl´ azquez b , M. Kowalczyk c , J.J. Ipus b , T. Kulik c , C.F. Conde b a Ins i u o de Ciencia de Ma e iales de Se illa, ICMSE CSIC-Uni e sidad de Se illa, C. Am´ e ico Vespucio 49, Se illa 41092, Spain b Dp o. Física de la Ma e ia Condensada, ICMSE-CSIC, Uni e sidad de Se illa, P.O. Box 1065, 41080 Se illa, Spain c Facul y o Ma e ials Science and Enginee ing, Wa saw Uni e si y o Technology, 141 Wołoska s ., 02-507 Wa saw, Poland ARTICLE INFO Keywo ds: Amo phous s uc u e Relaxa ion phenomena M¨ ossbaue spec oscopy Magne ic inhomogenei y Magne ocalo ic p ope ies ABSTRACT In his wo k, he elaxa ion o he amo phous s uc u e o mechanically alloyed Fe 70 Z 30 powde s has been analyzed h ough in e up ed hea ing amps below he de i i ica ion empe a u e. As a esul o such he mal ea men , Cu ie empe a u e and empe a u e a maximum magne ic en opy change cu es shi o highe empe a u es as he empe a u e o hea ing ea men inc eases. This e ec can be a ibu ed o bo h he elease o he s ess accumula ed in he amo phous powde du ing he milling p ocess and o he ini ia ion o nuclea ion o α -Fe c ys alli es, as i has been shown by M¨ ossbaue spec oscopy. 1. In oduc ion Magne ic p ope ies o Fe- ich amo phous alloys ha e ecei ed sig- ni ican a en ion in he esea ch communi y om bo h undamen al and echnological pe spec i es [1,2]. These ma e ials p esen a ypical magne ic phenomena, such as magne oelas ic beha io [3] o double ansi ion beha io [4], depending on Fe con en [5] and he local a omic o de [6]. Mo eo e , hese sys ems can be also conside ed as a p ecu so o he de elopmen o di e en in e me allics [7]. Fu he - mo e, hese amo phous so e omagne ic alloys ha e ecei ed conside able a en ion in he esea ch communi y ocused on magne- ocalo ic e ec , MCE, and magne ic e ige a ion a empe a u es close o oom empe a u e [8]. So magne ic amo phous alloys can be clas- si ied as magne ocalo ic ma e ials wi h a second o de magne ic an- si ion (SOPT). Al hough he MCE exhibi ed by hese sys ems is no eally in compe i ion wi h Gd (pa adigma ic ma e ial o magne ic e ige a- ion a oom empe a u e [9]) o sys ems wi h a i s o de magne ic ansi ion, such as Ni-based Heusle alloys [10], hey exhibi a eally educed magne ic hys e esis and an easily unable Cu ie empe a u e wi h small composi ional changes [11,12]. Fu he mo e, he ield dependence o MCE o hese sys ems is well es ablished [13]. Al hough amo phous alloys a e ypically p oduced by apid quenching echniques, he exis ence o wo eu ec ic poin s in he Fe-Z phase diag am [14,15] es ic s he capabili y o his echnique o p oduce amo phous alloys o speci ic composi ions, close o Fe 25 Z 75 and Fe 90 Z 10 . Thus, o he echniques ha e been p oposed o p epa e amo phous Fe-Z compounds in a b oade ange o composi ions, such as mechanical alloying o spu e ing echniques, which expand he p oduc ion o amo phous samples o a Fe con en o 30–80 a .% [16] and 20–90 a .% [17], espec i ely. The mechanical alloying echnique has been employed o p oduce many amo phous alloys [18] and, gene ally, leads o s ongly diso de ed sys ems. Consequen ly, he milled amo phous samples a e in a me a- s able s a e, which can induce di e en ans o ma ions du ing he mal ea men s, e en a empe a u es lowe han hose co esponding o he de i i ica ion p ocess. Al hough some wo ks pay a en ion o he Fe 70 Z 30 a .% amo phous alloy [5,19-21] and i s de i i ica ion p ocess [7], including some p e ious wo ks o he au ho s [22–24], he s udy o he e ec o he elaxa ion phenomena on he magne ic beha io o his alloy has no ye been pe o med. The pu pose o his s udy is o analyze he e ec o he elaxa ion phenomena o amo phous Fe 70 Z 30 powde s p epa ed by mechanical alloying on hei magne ic beha io . The e o e, o shed some ligh on he me as able cha ac e o hese samples, he p esen wo k is de o ed o analyze he he mal dependence o he magne ic p ope ies o he alloy submi ed o di e en he mal ea men s a empe a u es below he de i i ica ion empe a u e. The esul s ob ained in his s udy a e complemen a y o ea lie wo ks * The co esponding au ho . E-mail add ess: [email p o ec ed] (A.F. Manch´ on-Go d´ on). Con en s lis s a ailable a ScienceDi ec Jou nal o Non-C ys alline Solids jou nal homepage: www.else ie .com/loca e/jnonc ysol h ps://doi.o g/10.1016/j.jnonc ysol.2023.122267 Recei ed 23 Janua y 2023; Recei ed in e ised o m 2 Ma ch 2023; Accep ed 6 Ma ch 2023 Jou nal o Non-C ys alline Solids 609 (2023) 122267 2 o he au ho s on he Fe-Z amo phous alloys p epa ed by mechanical alloying in which se e al aspec s ha e been in es iga ed: i) he e olu- ion o Fe en i onmen s and he phase composi ion du ing mechanical amo phiza ion p ocess [25]; ii) he kine ics o he mechanical amo ph- iza ion [26]; iii) he in luence o milling ime on he magne ic p ope ies [27]; and i ) he he mal s abili y and he kine ics o c ys alliza ion [7]. 2. Expe imen al Amo phous alloy wi h Fe 70 Z 30 a .% composi ion was syn hesized by mechanical alloying. De ails on p epa a ion and a de ailed analysis o he mic os uc u e o he syn hesized powde s can be ound in e . [25]. A e 50 h o milling, mechanical alloying esul s in he alloy wi h amo phous s uc u e. To explo e he e ec o hea ing on he amo phous s uc u e, powde samples we e hea ed, a 10 K/min up o di e en maximum empe a u es in a di e en ial he mal analysis (DTA) Pe kin-Elme DTA7 uni unde A low. Th ee di e en maximum em- pe a u es we e eached in he expe imen s pe o med: 473, 573 and 673 K. Subsequen ly, he samples we e cooled down o oom empe a- u e inside he o en. Two echniques con i med he amo phous cha ac e o he powde : X- ay di ac ion using Cu-K α adia ion in a Rigaku MiniFlex di ac- ome e and DTA. T ansmission M¨ ossbaue spec a we e measu ed using a 57 Co(Rh) sou ce a oom empe a u e and i ed wi h NORMOS p o- g am [28]. Isome shi has been gi en ela i e o an α -Fe oil a oom empe a u e. Samples o M¨ ossbaue spec oscopy we e p epa ed by sp eading powde on a Fe- ee adhesi e ape in such a way ha he hickness o he sample is o he o de o ha o he Fe hin oil s anda d used o calib a ion. The e o e, hin abso be app oxima ion was used o he i ing o he spec a. Tempe a u e and magne ic ield dependen magne iza ion we e ob- ained using he ib a ing sample magne ome e s anda d op ion o a Physical P ope ies Measu emen s Sys em (PPMS, Quan um Design) be ween 100 and 400 K in he applied ield ange o ±1.5 T. Loose powde was packed in he VSM powde Sample Holde s. E ec o demagne izing ac o has no been conside ed in his s udy. 3. Resul s and discussion Fig. 1 depic s he XRD pa e ns aken a oom empe a u e om powde s hea ing up o he indica ed empe a u es below he de i i i- ca ion empe a u e, as obse ed in he inse . This inse shows he DTA scans o he as-milled powde a 10 K/min, whe e an onse empe a u e ∼920 K can be obse ed. The wo peaks de ec ed co espond o he o ma ion o he Fe 2 Z and Fe 23 Z 6 in e me allics [7]. Despi e o he hea ing ea men , he amo phous s uc u e is e ained, as can be in e ed by he exis ence o a b oad halo a 2θ∼43◦in all he s udied condi ions. In he case o 573 and 673 K annealing empe a u es, a small di ac ion peak begins o de elop loca ed a a ound 2θ∼45◦, associa ed wi h he (110) maximum di ac ion peak o he α -Fe phase. Al hough he XRD pa e n o he as-milled and 473 K annealing empe a u e do no exhibi he p esence o α -Fe c ys alli es in he sample, i has been shown he exis ence o esidual α -Fe nanoc ys als by M¨ ossbaue spec- oscopy a low empe a u es in he as-milled powde s (∼3% phase con ibu ion) [27]. The e omagne ic cha ac e o he amo phous ma- ix a empe a u es below oom empe a u e allows o a e omagne ic coupling be ween he esidual α -Fe c ys alli es and he isible Fig. 1. XRD pa e ns a oom empe a u e o Fe 70 Z 30 as-milled amo phous alloy and a e hea ing up o he ma ked empe a u es. Inse shows DTA cu es o he de i i ica ion o he as-milled amo phous alloy unde a cons an hea ing a e o 10 K/min. Cha ac e is ic empe a u es, onse , Tonse , and peak empe - a u es, Tpk, ha e been indica ed. Fig. 2. M¨ ossbaue spec a a oom empe a u e o amo phous samples a e hea ed up o he ma ked empe a u es. A.F. Manch´ on-Go d´ on e al. Jou nal o Non-C ys alline Solids 609 (2023) 122267 3 con ibu ion by M¨ ossbaue spec oscopy. The e o e, he appea ance o he (110) maximum di ac ion peak in he case o 573 and 673 K annealing empe a u e co espond o an inc ease o he c ys al size o hose emaining c ys alli es in he amo phous ma ix. Fig. 2 p esen s M¨ ossbaue spec a aken a oom empe a u e o he alloy powde s hea ed up o he ma ked empe a u es. As he annealing empe a u e inc eased, an inc ease o he peaks a ound ±4 and ±6 mm/ s can be obse ed, indica ing he de elopmen o a magne ically-o de ed phase a oom empe a u e. Consequen ly, wo componen s ha e been employed o i he spec a, a quad upola dis ibu ion and a e o- magne ic sex e . While he i s pa amagne ic con ibu ion can be asc ibed o he amo phous phase, he e omagne ic si e can be associ- a ed wi h he o ma ion o he α -Fe phase, cha ac e ized by a hype ine ield o abou 33 T. The quad upole spli ing dis ibu ions, P(QS),a e displayed in Fig. 3, which exhibi he same beha io o all he samples, wi h a non-ze o p obabili y o QS=0 mm/s. The ob ained hype ine pa ame e s om he spec a i ing ha e been collec ed in Table 1. The mean alue o quad upole spli ing, 〈QS〉,is close o he alues p e i- ously epo ed o as-milled Fe 70 Z 30 alloy 〈QS〉=0.53±0.07 mm/s [25]. Despi e he de elopmen o he α -Fe phase and he co esponding Fe impo e ishmen o he amo phous alloy, no signi ican e ec s on he quad upola dis ibu ion ha e been de ec ed. F om hese i s, an e iden inc ease o he e omagne ic con ibu ion wi h he inc ease o he empe a u e o ea men can be obse ed, eaching a alue o 12% o he o al Fe a oms in α -Fe si es o he case o he annealed powde a 673 K (assuming pu e α -Fe, his yields 8.5 a omic ac ions o he c ys alline phase). E en hough he α -Fe phase was no de ec ed by XRD, he exis ence o his phase is e iden by he M¨ ossbaue spec a o he analyzed powde s. The o ma ion o he α -Fe phase a empe a u es lowe o he c ys alliza ion empe a u e o he amo phous alloy is due o he exis ence o esidual α -Fe c ys als a e he amo phiza ion p ocess. Al hough hese nanoc ys als can no be de ec ed by XRD echnique a oom empe a u e, hei exis ence is clea ly con i med when he samples a e analyzed by M¨ ossbaue spec oscopy a empe a u es below oom empe a u e. In ac , a oom empe a u e, he pa amagne ic cha ac e o he amo phous ma ix p e en s he coupling o he dissemina ed α -Fe nanoc ys als. Mo eo e , i is well known ha M¨ ossbaue spec oscopy is a mo e p ecise echnique han XRD o iden- i y Fe- ich phases [25], pa icula ly in such cases as he one analyzed he e, whe e he amo phous halo can jeopa dize he p esence o iny bu b oad c ys alline maximum. On he o he hand, an inc ease o he hy- pe ine ield o he sex e assigned o he α -Fe phase ha e been also de e mined. This e olu ion can be associa ed wi h he dec ease o Z a oms in he neighbo hood o he α -Fe phase. I has been shown ha he hype ine ield o Fe is s ongly a ec ed by he p esence o o he a oms as a nea neighbo s (e.g. ΔB h ~−3 T o a non-magne ic a om in he wo i s shells [29]). Fig. 4a illus a es he magne iza ion dependence on he empe a u e o he s udied powde s when an ex e nal magne ic ield o 100 Oe is applied. On cooling, he he momagne ic cu es a e cha ac e ized by a sudden inc ease o he magne iza ion a ound 240 K, co esponding o he pa amagne ic o e omagne ic phase ansi ion o he amo phous phase. I indica es he pa amagne ic beha io o he amo phous powde a oom empe a u e, in ag eemen wi h he M¨ ossbaue spec oscopy Fig. 3. P obabili y dis ibu ion o quad upole spli ing o he s udied powde s. Table 1 Hype ine pa ame e s o he s udied he mally ea ed amo phous samples. A ea (%) is he ela i e con ibu ion o he componen , and B h and δ a e he alues o he hype ine magne ic ield and he isome shi o he e omagne ic si e, espec i ely. <Qs>is he mean alue o he quad upola shi . Annealing empe a u e (K) Componen A ea (%) B h ±0.1 (T) δ±0.02 (mm/s) <Qs>±0.05 (mm/s) 473 Quad upola dis ibu ion 94 – −0.15 0.49 α -Fe si e 6 31.6 0.06 – 573 Quad upola dis ibu ion 90 – −0.14 0.47 α -Fe si e 10 32.5 0.04 – 673 Quad upola dis ibu ion 88 – −0.14 0.52 α -Fe si e 12 32.6 0.02 – Fig. 4. a) Tempe a u e dependence o he speci ic magne iza ion o Fe 70 Z 30 as- milled amo phous alloys and a e hea ing up o he ma ked empe a u es unde an applied magne ic ield o 100 Oe. b) Co esponding dM/dT cu es. Inse shows he e olu ion o he Cu ie empe a u e ob ained as he minima o dM/dT cu es. The co esponding da a o he as-milled sample has been included o compa ison. A.F. Manch´ on-Go d´ on e al. Jou nal o Non-C ys alline Solids 609 (2023) 122267 4 esul s. I has been shown ha a signi ican change in he magne iza ion o as-milled powde s occu s only when he powde s a e hea ed up abo e 800 K [7,30]. No mo e ansi ions ha e been obse ed in he ange o empe a u e and magne ic ields applied o he powde s. Howe e , signi ican a ia ions in he magne iza ion can be obse ed wi h he inc ease in he empe a u e o he he mal ea men s. In his sense, magne iza ion does no all o ze o in none o he cases analyzed due o he exis ence o a ce ain α -Fe phase con ibu ion, which has a much highe Cu ie empe a u e han hose o he amo phous one (speci ic magne iza ion a 400 K inc eases om 4 o 13 kA/m as annealing empe a u e inc eases om 473 o 573 K in ag eemen wi h he inc ease obse ed in he e omagne ic a ea om M¨ ossbaue spec oscopy). As he annealing empe a u e inc eases, he d op o he magne iza ion a he Cu ie empe a u e dec eases because o he g ow h o he α -Fe ac ion, i.e. he di e ence be ween he magne iza ion be o e and a e he Cu ie ansi ion o he amo phous phase is educed wi h he he mal ea men , in ag eemen wi h he e olu ion o he M¨ ossbaue i s. Acco dingly, he magne iza ion a low empe a u es dec eases due o he Fe deple ion o he amo phous phase as he annealing empe a u e inc eases. The applied ield o 100 Oe ( o measu e he cu es p esen ed in Fig. 4a) is high enough o exceed he coe ci e ield bu low enough o allow he obse a ion o a su icien ly poin ed magne ic ansi ion a he Cu ie empe a u e, TC. This pa ame e has been es ima ed as he in lexion poin o he magne iza ion as a unc ion o empe a u e, (minimum in dM/dT cu es, see b). Al hough he ange o empe a u e a which dM/dT de lec s om ze o is conside able, ypical o sys ems in which a Cu ie empe a u e dis ibu ion exis s, a clea endency can be obse ed: TC inc eases wi h he inc ease o he annealing empe a u e. In ac , i is well known ha TC is s ongly dependen on Fe con en and he local a omic o de in Fe-Z amo phous compounds [31,32]. In his sense, i has been epo ed ha in Fe-based amo phous alloys, wi h non-magne ic a om subs i u ion, TC inc eases as Fe con en dec eases in he alloy [30]. The inc ease o TC, in his composi ion ange, is due o a d op o he in e a omic dis ances o o an inc ease o he Fe con en . Howe e , he he mal ea men o he sample in ol es an inc ease om 6 o 12% o α -Fe phase, as de e mined by M¨ ossbaue spec oscopy (see Table 1). The e o e, he amo phous ma ix o he annealed powde s exhibi s a sligh impo e ishmen o he Fe con en . I is e i ied by he enhancemen o he magne iza ion emaining abo e he TC o he Fig. 5. Magne ic hys e esis loops, aken a di e en empe a u es om 100 K o 300 (100, 150, 200, 220, 240, 250, 260, 280 and 300 K) o he mechanically alloyed powde s a e hea ing up o he indica ed empe a u es. Inse s show he low ield egion o he hys e esis loops a 100 and 300 K. Fig. 6. Pa ame e s ob ained om he app oach o sa u a ion o he magne i- za ion cu es o Fig. 5 o he powde s hea ed up un il he indica ed empe a- u es. a) Speci ic sa u a ion magne iza ion and dM S/dT cu es (inse ), whe e Tin co esponds o he minimum. b) Pa amagne ic suscep ibili y cu es om he law o app oach o sa u a ion. Lines a e guide o he eyes. A.F. Manch´ on-Go d´ on e al. Jou nal o Non-C ys alline Solids 609 (2023) 122267 5 amo phous s uc u e (see Fig. 4a). Mo eo e , wi h he inc ease o he annealing empe a u e, he dM/dT cu es become na owe . This ac could be asc ibed o he elease o he s esses accumula ed in he amo phous powde du ing he milling p ocess and he educ ion o he impu i ies due o he nuclea ion o α -Fe c ys alli es. Fig. 5 shows he hys e esis loops o he s udied powde s eco ded a di e en empe a u es om 100 o 300 K. As expec ed, all he samples exhibi a simila end, cha ac e ized by a quick inc ease o he magne iza ion a low ields. This beha io o he hys e esis loops ag ees wi h he expec ed so -magne ic na u e o he s udied alloys. The ex ac ed alues o sa u a ion magne iza ion, MS(T), and he pa amagne ic suscep ibili y, χ p(T), o he hys e esis loops a e displayed in Fig. 6. These pa ame e s ha e been de e mined by i ing he expe - imen al high- ield magne iza ion cu es ( μ 0H≥1 T) o he linea e sion o law o app oach o sa u a ion [33]. MS(T)cu es all wi h he e o- lu ion o he empe a u e due o he e o-pa amagne ic ansi ion o he amo phous phase. The g ow h o MS as he annealing empe a u e in- c eases is in ag eemen wi h he g adual ise o he α -Fe phase in he sample, wi h a highe magne iza ion han ha o he amo phous s uc u e. These esul s a e in ag eemen wi h hose ob ained by M¨ ossbaue spec oscopy. The inse o he Fig. 6a depic s he dMS /dT cu es, whose minimum, Tin , is usually app oxima ed o he Cu ie empe a u e. On he o he hand, χ p(T)cu es exhibi a maximum, T χ p peak, ha sligh ly shi s o highe empe a u es wi h he inc ease o he annealing empe a u e. The di e gence be ween Tin and T χ p peak ound in ou esul s indica es he p esence o a dis ibu ion o ansi ion em- pe a u es [34]. Al hough a me hod o de e mine he pa ame e s o his dis ibu ion was ecen ly p oposed using Tin and T χ p peak [34], bo h pa- ame e s need o be e de ined, a oiding a quan i a i e analysis o he dis ibu ion. Fig. 7 p esen s he magne ic en opy change, ΔSM, o he s udied samples as a unc ion o empe a u e o a maximum applied ield change o 1 T. The M(T,H)da a we e ob ained on cooling cycles as a unc ion o empe a u e a each magne ic ield, being a empe a u e in e al o 1 K and he ΔSM was de e mined using a nume ical app ox- ima ion o he Maxwell ela ion. Demagne izing ield has no been aken in o accoun and a negligible e ec on ΔSM(T)cu es is assumed [22]. No signi ican di e ences can be obse ed be ween he di e en sam- ples, eaching a maximum alue o abou 0.45 Jkg −1 K −1 a 233 K o he sample as-milled. This maximum alue sligh ly shi s o highe em- pe a u es wi h he inc ease o he annealing empe a u e, in ag eemen wi h he esul s p esen ed abo e. Al hough he ob ained alues o ΔSM a e simila o hose ound in he li e a u e o samples wi h he same composi ions ob ained by mechanical milling, he obse ed alues a e modes when hey a e compa ed wi h amo phous ibbon samples o a simila composi ion p oduced by apid quenching echniques (see able 2) [35,36]. I is also no ed ha he wid h o ΔSM(T)cu es dec eases o apidly quenched samples, sugges ing a s onge inhomogenei y in he samples p epa ed by milling [37]. Recen ly, he C-doping o Fe-Z amo phous alloys ha e been in es iga ed in o de o imp o e he mag- ne ocalo ic esponse o hese ma e ials h ough uning he Cu ie em- pe a u e close o oom empe a u e and achie ing an enhancemen o ΔSM [38]. 4. Conclusions Relaxa ion o he amo phous s uc u e o Fe 70 Z 30 amo phous alloy p epa ed by mechanical alloying has been in es iga ed by means o annealing a empe a u es below he de i i ica ion empe a u e. The annealing ea men s e ain he amo phous s uc u e o he alloy, de ec ed by X- ay di ac ion. Howe e , hey induce he ini ia ion o nuclea ion o α -Fe c ys alli es, as es ima ed by M¨ ossbaue spec a, which need one e omagne ic and one pa amagne ic con ibu ion o be suc- cess ully i ed. Consequen ly, he amo phous alloy su e s a deple ion in Fe con en . This ac is e i ied by he augmen a ion o he magne iza- ion pe sis ing abo e he amo phous alloy’s e omagne ic- pa amagne ic ansi ion and he Cu ie empe a u e inc ease. Finally, he na owing o he de i a i e cu es o he magne iza ion wi h he annealing ea men sugges s ha , despi e he pa i ioning o Fe o he nuclea ion o he α -Fe phase, he amo phous phase o he annealed samples is mo e chemically and s uc u ally homogeneous han ha o he o iginal p ecu so . CRediT au ho ship con ibu ion s a emen A.F. Manch´ on-Go d´ on: Concep ualiza ion, Da a cu a ion, In es i- ga ion, Fo mal analysis, Resou ces, W i ing – o iginal d a . J.S. Bl´ azquez: Concep ualiza ion, Me hodology, Supe ision, W i ing – e- iew & edi ing, Resou ces. M. Kowalczyk: Da a cu a ion, Supe ision, Fig. 7. Va ia ion o ΔS M wi h empe a u e (calcula ed o 1 T ield change) o he s udied amo phous alloys close o Cu ie empe a u e. Inse shows he e olu ion o maximum o ΔSM wi h empe a u e. Table 2 Expe imen al alues o |ΔSM| o FeZ based amo phous alloys p epa ed by di e en echniques. Composi ion Technique Tann (K) TC (K) ΔH (T) |ΔSM|(Jkg −1 K −1 ) Re e ence Fe 70 Z 30 Mechanical alloying as-milled 235 1.0 0.45 [12] 473 238 1.0 0.40 This wo k 573 240 1.0 0.40 This wo k 673 244 1.0 0.38 This wo k Fe 70 Z 30 Mechanical alloying 244 1.5 ∼0.4 [23] Fe 91 Z 9 Rapid quenching 233 1.5 1.22 [39] Fe 90 Z 10 Rapid quenching 245 1 0.87 [33] Fe 89 Z 11 Rapid quenching 263 1.8 1.3 [34] Fe 93 Z 7 Spu e ing 160 1.5 ∼0.7 [38] (Fe 93 Z 7 ) 0⋅89 C 0.11 Spu e ing 311 1.5 ∼1 Fe 88 Gd 2 Z 10 Rapid quenching 285 1.5 1.4 [40] A.F. Manch´ on-Go d´ on e al. Jou nal o Non-C ys alline Solids 609 (2023) 122267 6 W i ing – e iew & edi ing. J.J. Ipus: Da a cu a ion, Supe ision, W i ing – e iew & edi ing. T. Kulik: Resou ces, W i ing – e iew & edi ing. C.F. Conde: Resou ces, Me hodology, Supe ision, W i ing – e iew & edi ing. Decla a ion o Compe ing In e es The au ho s decla e ha hey ha e no known compe ing inancial in e es s o pe sonal ela ionships ha could ha e appea ed o in luence he wo k epo ed in his pape . Da a a ailabili y No da a was used o he esea ch desc ibed in he a icle. Acknowledgemen s This wo k was suppo ed by he PAI o he Regional Go e nmen o Andalucía and by Jun a de Andalucía-Conseje ía de T ans o maci´ on Econ´ omica, Indus ia, Conocimien o y Uni e sidades (p oyec P oyEx- cel_00360). VI and VII-PPUS om Uni e si y o Se ille is also acknowledged. Re e ences [1] M.E. McHen y, M.A. Willa d, D.E. Laughlin, Amo phous and nanoc ys alline ma e ials o applica ions as so magne s, P og. Ma e Sci. 44 (4) (1999) 291–433. [2] K. 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