Aluminium – Iron – Siliconextras.springer.com/2005/978-3-540-23118-9/00400011a2/... · Aluminium – Iron – Silicon Gautam Ghosh Literature Data ... where xAl is the atomic

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Landolt-BörnsteinNew Series IV/11A2

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Al–Fe–Si

Aluminium – Iron – Silicon

Gautam Ghosh

Literature Data

The system contains many technologically important alloys, such as foil and sheet products for foodpackaging, capacitors, lithographic printing sheets, magnetic alloys for transformer. Furthermore, iron andsilicon, originating from bauxite ore and anode material, are present in nearly all industrial Al-alloys.Metallurgical grade silicon also contains, among others, aluminum and iron as impurities. Due to thesereasons, there are numerous experimental studies on the phase equilibria of the ternary system, the resultsof which have been reviewed from time to time [1934Fue, 1937Ser, 1943Mon, 1950Gme, 1952Han,1959Phi, 1968Dri, 1981Riv, 1981Wat, 1985Riv, 1987Pri, 1988Ray, 1992Gho, 1992Zak, 1994Rag,2002Rag]. The system is characterized by a large number of ternary phases, both stable and metastable, andat least nineteen ternary invariant reactions during solidification which impart difficulties in establishing thephase equilibria of the system. The difficulties are further augmented by the effects of metastability,impurity elements, incomplete reactions, undercooling, and many solid-state reactions which are not wellunderstood.Earlier works by [1923Dix, 1923Han, 1923Wet, 1924Fus, 1934Roe, 1941Pan] were mostly on theobservation of microstructures of dilute Al-alloys. [1951Ran] determined the phase boundaries of theAl-corner at 475°C by diffusional anneal technique. Due to extensive results [1927Gwy, 1933Nis, 1936Jae,1937Ura, 1943Phi, 1951Hol, 1951Now, 1967Mun, 1987Gri1, 1987Ste], the phase equilibria of theAl-corner are well established. The first comprehensive study of phase equilibria of the entire system was performed by [1940Tak]. Theyused electrolytic iron, pure aluminium and metallic silicon (unspecified purity). Over 150 ternary alloyswere prepared using master alloys of selected compositions in an arc furnace, under hydrogen atmospherewith NaCl as flux on the molten surface of the alloys, followed by cooling at a rate of 2 to 3 K per 5 to 10sec. In some cases, in order to confirm and identify solid-state reactions, the cooling curves weresupplemented by heating runs. [1940Tak] employed metallography, thermal, X-ray, magnetic anddilatometric analyses to establish the phase equilibria. They reported six ternary phases, and all form byperitectic reactions. They also presented an extensive set of several vertical sections from 500°C up to theliquidus temperature. Based on these results, [1981Riv] constructed a probable isothermal section at 600°C.The Fe-corner was extensively studied by [1968Lih] up to 50 at.% Al and 35 at.% Si by DTA,thermo-magnetometry, microhardness and X-ray diffraction. The phase equilibria involving ordered anddisordered phases in Fe-rich alloys were determined by [1982Miy] and [1986Miy] in the temperature rangeof 450 to 700°C using transmission electron microscopy. Recent investigations of the Al-corner, for alloys up to 14 at.% Si and 35 at.% Fe, are due to [1987Gri1] and[1987Ste]. They used thermal analysis, X-ray diffraction and electron probe microanalysis to establish theliquidus surface, and isothermal sections at 570 and 600°C. These results were slightly modified by[1987Pri] to make them consistent with the thermodynamic rules of phase diagram construction. [1981Zar] reported ten ternary phases, and an isothermal section at 600°C. [2001Kre] determined a partialisothermal section at 550°C. About 100 alloys, containing up to 50 at.% Fe and 50 at.% Si, were used. Thephase equilibria were established by extensive use of X-ray diffraction, EDS analysis of the phases, andoptical metallography.Thermodynamic datasets of the ternary system were assessed by [1994Ang, 1998Kol, 1999Liu].

Binary Systems

The Al-Si binary phase diagram is accepted from [2003Luk]; the Al-Fe binary phase diagram is acceptedfrom [2003Pis]; and the Fe-Si binary phase diagram is accepted from [1982Kub]. In the Al-Fe system, ithas been reported that Fe4Al13 melts congruently at 1152°C [1986Len] which confirms earlier finding by[1960Lee].

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Solid Phases

As far as the binary intermediate phases are concerned, only those appearing in the equilibrium phasediagrams are considered here. For example, direct chill-cast of commercially pure Al-alloys are reported tocontain Al-Fe intermediate phases that are not present in the equilibrium phase diagram [1977Sim,1982Wes, 1985Don2, 1986Liu1, 1986Liu2, 1987Cha, 1987Skj1, 1987Skj2, 1987Ste, 1988Cha, 1988Liu2].Therefore, they are not considered in constructing the ternary phase diagrams.At 550°C, the solubility of Fe and Si in (Al) is less than 1 at.% [2001Kre], and that of Fe and Al in (Si) isextremely small.The Fe4Al13 phase is reported to dissolve 0.8 mass% Si [1955Arm], 0.2 mass% Si [1967Sun], 1.0 mass%Si [1984Don], 2.9 mass% Si [1987Skj1], up to 6.0 mass% Si at 600°C [1987Ste], and 4 at.% Si at 550°C[2001Kre]. This is associated with an increase in the a-lattice parameter and a decrease in the b-latticeparameter; whereas no significant changes in the c-lattice parameter and $ were detected [1987Ste]. Thecomposition dependence of a- and b-lattice parameters in Fe4Al13 is expressed by [1987Ste] asa (in pm) = [email protected]@WSib (in pm) = [email protected]@WSiwhere WFe and WSi are the mass% of Fe and Si, respectively. A detailed crystallographic analysis of theFe4Al13 phase, by means of convergent beam electron diffraction and high resolution electron microscopy,has been performed by [1987Skj3]. Lattice images revealed that the Fe4Al13 crystals are divided into tinydomains (few thousand pm) which are separated by lattice displacements such as stacking faults [1987Skj2,1987Skj3]. At 550°C, FeAl2 dissolves about 1 at.% Si, and Fe2Al5 dissolves about 2 at.% Si [2001Kre].Initial studies showed that the FeSi2(h) phase dissolves up to about 0.5 mass% Al [1961Sab, 1965Sab,1965Skr, 1968Sab1, 1968Sab2] which is accompanied by a small increase in both the a- and c-latticeparameters. However, later it was found that FeSi2 dissolves up to 10 at.% Al [1994Ang, 1995Gue3]. TheFeSi phase also dissolves substantial amount of Al [1996Szy, 1998Dit], and at 550°C it is about 10 at.%with Al substituting Si [2001Kre]. The ambient temperature lattice parameters of FeSi, FeSi2(h) andFeSi2(r) as functions of Al-content were reported by [1996Szy]:For FeSi: a (in pm) = 448.1+5.4xAlFor FeSi2(h): a (in pm) = 269.1+17.9xAl c (in pm) = 515.7+30.2xAlFor FeSi2(r): a (in pm) = 986.6+7.3xAl b (in pm) = 778.7+10.3xAl c (in pm) = 782.1+27.6xAlwhere xAl is the atomic fraction of Al. The Fe3Al and Fe3Si phases form a continuous solid solution. The lattice parameter of the alloys alongFe3Al-Fe3Si and Fe73Al27-Fe73Si27 sections and also for the commercial SENDUST and ALSIFER 32alloys were determined systematically and accurately by [1979Cow]. The composition dependence of thelattice parameter can be expressed as:Along the Fe3Al-Fe3Si sectiona (in pm) = 565.54+12.846@[email protected]@W3 = 565.54+12.776@[email protected]@C3

where W = mass fraction of Fe3Al and C = mole fraction of Fe3Al.Along the Fe73Al27-Fe73Si27 sectiona (in pm) = 564.462+11.964@W [email protected]@W3 = 564.462+11.915@C [email protected]@C3

where W = mass fraction of Fe73Al27 and C = mole fraction of Fe73Al27.[1979Cow] attributed a small, but consistent deviations from the linear dependence on composition, alongboth sections, to the incomplete ordering as Al is replaced by Si. [1979Bur] also reported limited latticeparameter data along Fe3Al-Fe3Si section which are in reasonable agreement with those of [1979Cow], but[1979Bur] assumed a linear dependence of lattice parameter on composition (see also [1977Nic1],[1977Nic2]). [1968Lih] reported lattice parameters of ternary alloys up to 30 at.% Si and 47 at.% Al at 20,500, 600 and 900°C. [1946Sel] also measured the lattice parameter of ternary alloys up to 18 mass% Si and13 mass% Al. The lattice parameter of Fe3(Al,Si) containing about 10 mass% Al and 5 mass% Si is reported

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to be 570 ± 3 pm [1978Xu]. The lattice parameter of an Fe-5.5 mass% Al-9.7 mass% Si alloy is reported tobe 568.4 pm after water quenching and 568.54 pm after annealing for 24 h at 600°C.The complexity of phase equilibria of the Al-Fe-Si system is primarily due to the occurrence of manyternary phases, and the associated metallurgical reactions during solidification and during heat treatments.While some of these ternary phases are stable, many are metastable. In recent years, detailedcrystallographic characterization of the stable phases have been performed; however, the currentcrystallographic data of many metastable ternary phases are far from being complete. The difficulties ofcomplete crystallographic characterization of these phases are due to (i) the occurrence of several phasesover a relatively narrow composition range in the Al-corner, (ii) the complex crystal structure along withthe presence of high density of planar defects in ternary phases, (iii) the order-disorder reactions in theFe-corner, (iv) many invariant reactions which under normal experimental conditions (both duringsolidification and during heat treatments) do not undergo completion, and (v) the effect of heterogeneousnucleation on the phase selection during solidification. In the past seven decades a large number of ternaryphases in the Al-Fe-Si system have been reported. A chronological survey of these ternary phases is givenin Table 1, where it may be noted that some of the results are still controversial. Nine ternary phases are accepted for the construction of phase diagrams. These are labeled as J1 to J10.Among these, [1940Tak] reported six ternary phases, four of which (J2, J4, J5, and J6) could be identifiedwithout much difficulty. Their investigation was mainly based on thermal analysis and microstructuralexamination, supplemented by limited X-ray diffraction. Single crystal structure determinations have beencarried out for J1 [1996Yan], J3, [1989Ger2], J4, [1969Pan, 1995Gue1], J6, [1994Rom], J7, [1995Gue2]and J10, [1989Ger1]. The details of the crystal structures and lattice parameters of the solid phases are listedin Table 2. The composition ranges of the equilibrium ternary phases reported by different authors areplotted in Fig. 1. It may be noted that while most of the composition ranges are isolated from each other,there are overlapping composition ranges among J2, J3 and J10 phases.The J1-phase has monoclinic structure, and its composition has been corrected from Fe3Al3Si2 to Fe3Al2Si3[1996Yan]. [2001Kre] established that the previously reported J1 and J9 [1992Gho] are actually the samephase. The J1-phase corresponds to the K1-phase of [1940Tak] and the E-phase of [1981Zar], and J9corresponds to the D-phase of [1981Zar]. [2001Kre] also confirmed triclinic structure [1996Yan] of J1/J9.At 550°C, J1/J9 coexists with Fe2Al5, Fe4Al13, "2, FeSi, J2, J3, J7, J10, and possibly J8 [2001Kre].[1981Zar] represented the homogeneity range of J2-phase (the K-phase) as Fe22Al52-63Si15-26, which mostlikely corresponds to the K3-phase of [1940Tak]. [2001Kre] represented its homogeneity range asFe(Al1-xSix)7, with 0.2 # x # 0.33. As seen in Table 2, three crystal structures of J2 have been reported.[2001Kre] indexed the X-ray diffraction pattern of J2 using the monoclinic unit cell proposed by[1967Mun]. At 550°C, J2 coexists with Fe4Al13, J1/J9, J3, J4, J5, J6 and J7 [2001Kre].The J3-phase corresponds to the K2-phase of [1940Tak] and the G-phase of [1981Zar], and it has negligiblehomogeneity range [2001Kre]. The composition of J3 is represented as FeAl2Si [1981Zar], but EDSanalysis of [2001Kre] gave Fe25Al56±1Si19±1, or Fe(Al1-xSix)3, with x = 0.25. On the other hand,[1989Ger2] reported its composition as Fe(Al1-xSix)3, with x=0.33 based on XRD analysis. [2001Kre]suggested that it is impossible to detect such a small difference in Al/Si-ratio based on XRD analysis. Itsstructure has been confirmed to be orthorhombic [1974Mur, 1981Zar, 1989Ger2, 2001Kre]; however, thereis a scatter in the lattice parameter values. At 550°C, J3 coexists with Fe4Al13, J1/J9, J2 and J10 [2001Kre].The J4-phase corresponds to the K4-phase of [1940Tak] and the A-phase of [1981Zar]. It is single phase atthe composition Fe(Al0.6Si0.4)5 [2001Kre]. The tetragonal structure of the J4 phase was first reported by[1936Jae], and subsequently confirmed by several others [1950Phr, 1969Pan, 1974Mur, 2001Kre]. At550°C, J4 coexists with (Si), J2, J6 and J7 [2001Kre].The J5-phase corresponds to the K5-phase of [1940Tak] and the M-phase of [1981Zar]. Often, it is alsodesignated as "-AlFeSi. Its stoichiometry may be described as Fe46(Al0.875Si0.125)200-x, with x = 7[2001Kre]. The hexagonal structure of the J5 phase was first reported by [1953Rob], and subsequentlyconfirmed by [1967Mun, 1975Bar, 1977Cor, 1977Hoi, 1987Gri2, 1997Vyb, 2001Kre]. Earlier studies[1950Phr, 1952Arm, 1955Arm, 1967Coo] reported a cubic structure of J5, but it was attributed to traces(.0.3 mass%) of dissolved transition metals such as Mn or Cu that might have stabilized the cubic symmetry

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at the expense of the hexagonal structure [1967Sun, 1967Mun]. At 550°C, J5 coexists with (Al), Fe4Al13,J2, and J6 [2001Kre].The J6-phase corresponds to the K6-phase of [1940Tak] and the L-phase of [1981Zar]. Often, it is alsodesignated as $-AlFeSi. Its stoichiometry is FeAl4.5Si. Despite numerous studies, the crystal structure of J6is still controversial. While the X-ray diffraction studies reported its structure to be monoclinic [1950Phr,1954Spi, 1955Obi, 1975Bar, 1994Mur, 1994Rom, 1996Mur, 1997Vyb, 2001Kre], convergent beamelectron diffraction studies found that J6 is orthorhombic [1993Car, 2000Zhe]. In fact, [2000Zhe] did notfind any monoclinic phase in their electron microscopic investigation. They concluded that themisinterpretation of X-ray diffraction data indexed by a monoclinic cell may be due to intergrowth ofdifferent phases, and a high density of planar defects. At 550°C, J6 coexists with (Al), (Si), J2, J4 and J5[2001Kre].[1951Pra1] correlated the formation of J5 and J6 with the electron-to-atom ratio. [1979Mor] analyzed thecomposition of the intermetallic phases by electron microprobe technique and grouped them into twocategories based on the size and Fe/Si ratios which can be matched with the J5 and J6 phases. However,[1979Mor] reported 'indeterminate' particles having intermediate size and Fe/Si ratios between 2.75 and2.25. [1977Igl] postulated that the J5 phase is metastable and can replace the J6 phase at cooling ratesgreater than 200 K/min. [1985Suz] and [1987Nag] reported Mössbauer spectra of the J5 and J6 phases, theformer gave a relatively complex spectrum, and the latter gave a simpler one. The J7-phase corresponds to the B-phase of [1981Zar], and it has negligible homogeneity range [2001Kre].Based on the EDS data, the stoichiometry of J7 is Fe25Al45Si30, or Fe(Al1-xSix)3, with x = 0.4 [2001Kre].On the other hand, based on XRD data [1995Gue2] proposed the stoichiometry of J7 as Fe2Al3Si3, orFe(Al1-xSix)3, with x = 0.5, which reflects a discrepancy in Al/Si-ratio. Nevertheless, the monoclinicstructure of J7 reported by [1995Gue2] was also confirmed by [2001Kre]. The observation of Fe5Al8Si7[1994Ang] most likely corresponds to J7 [2001Kre], based on the assumption of a composition shift similarto J1, even though [1994Ang] did not report its crystal structure. At 550°C, J7 coexists with (Si), J1/J9, J2,J4 and J8 [2001Kre].The J8-phase corresponds to the C-phase of [1981Zar]. Its stoichiometry may range from Fe(Al1-xSix)2,with x = 0.5 [1981Zar] to Fe(Al1-xSix)2, with x = 0.67 [1996Yan]. It has orthorhombic structure [1996Yan,2001Kre]. The observation of Fe5Al5Si6 [1994Ang] most likely corresponds to J8 [2001Kre], based on theassumption of a composition shift similar to J1, even though [1994Ang] did not report its crystal structure.The J10-phase corresponds to the F-phase of [1981Zar] with stoichiometry Fe25Al60Si15. [1981Zar]reported that its structure in as-cast alloy is different from annealed condition, which was later confirmedby [1987Ste]. The hexagonal structure of J10 is prototypical of either Co2Al5 or Mn3Al10. [1989Ger1]reported Mn3Al10-type structure of J10 annealed at 600°C, while [2001Kre] reported the same structure inas-cast alloy. At 550°C, J10 coexists with Fe4Al13, J1/J9 and J3 [2001Kre].Recent investigations of precipitates in commercial Al alloys, by means of TEM/STEM, EDAX, and highresolution electron microscopy, have revealed a wide variety of precipitate crystal structures, latticeparameters and compositions [1982Wes, 1984Don, 1985Don1, 1985Don2, 1985Gri, 1985Liu, 1986Liu1,1986Liu2, 1987Cha, 1987Czi, 1987Skj1, 1987Ste, 1987Tur, 1988Ben2, 1988Cha] which can not begrouped together (for details see Table 1). In this assessment, these phases are considered to be metastable.In the absence of detailed crystallographic data, a classification of these metastable phases based on thecrystal system is proposed in Table 3. [1987Nag] and [1987Tur] found that the compositions of theintermediate phases and the phase transformations that take place during high temperature annealing dependon the Fe/Si ratio of the alloy. [1986Liu2] reported three different kinds of precipitates, in dilute Al-Fe-Sialloys, formation of which is reported to be a function of Fe/Si ratio, alloy purity, solidification rate and heattreatment. These factors probably explain the occurrence of so many ternary phases as reported by differentauthors. The principles governing the substitution of Al by Si in the ternary intermediate phases have beendescribed by [1989Tib]. The composition ranges of the metastable phases are plotted in Fig. 2. Compared to the equilibrium ternaryphases, the scenario here is much more complex. Virtually all metastable phases have overlappingcomposition range between 25 to 35 mass% Fe and 0 to 11 mass% Si. Besides crystalline metastable phases,

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the formation of amorphous phases in a number of Al-Fe-Si alloys has also been reported [1986Dun,1987Ben, 1988Ben1].

Order-Disorder Phase Transitions

There have been extensive studies of order-disorder transitions of Fe-rich ternary alloys, bothexperimentally and theoretically. Mutual solid solubility between Fe3Al and Fe3Si is well-established. Thesolid solubility and the magnetic behavior of Fe3(Al, Si) was correlated with electron-atom ratio [1977Nic1]and [1977Nic2]. The existence of the ordered phases "1 (Fe3Al and Fe3Si which have D03 or BiF3 typeorder) and "2 (FeAl and FeSi which have B2 or CsCl type order) along the Fe3Al-Fe3Si section was studied[1969Pol, 1973Kat] by means of high temperature X-ray diffraction and recording the disappearance of D03superlattice {111} and {200} reflections as a function of temperature and composition. [1946Sel] measuredthe lattice parameter of alloys up to 13 mass% Al and 18 mass% Si and observed an inflection point in thelattice parameter vs composition curve which was attributed to the ordering reaction and the formation ofFe3(Al,Si) having D03 superstructure. This was further supported by specific heat measurements as afunction of Si/Al ratio by [1951Sat], who found the reaction is accompanied by a small change in Gibbsenergy suggestive of a second-order reaction. However, with the addition of Si in Fe3Al the orderingenergies increase monotonically [1973Kat]. The order-disorder transitions along Fe3Al-Fe3Si was furtherstudied by transmission electron microscopy (TEM) [1982Cha] and by magnetic method [1986Tak].However, there is still some controversy regarding the sequence of ordering transitions along this section.Previous studies by [1969Pol] and [1973Kat] indicate that the sequence of ordering reaction (on cooling) isalways ("Fe)º"2º"1 along Fe3Al-Fe3Si section. However, recent studies by [1982Cha] and [1986Tak]indicate that substitution of more than 50% of the Al atoms by Si atoms ("Fe) transforms directly into D03structure. [1984Mat] studied two kinds of processes of ordering with phase separation, "2º("Fe+"1) and"1º("Fe+"1), in an Fe-6Fe-9Si (at.%) alloy using X-ray diffraction and transmission electron microscopy.Single phase "1 and "2 structures were retained by quenching the alloy from 700 and 900°C, respectively.The results of [1969Pol] and [1973Kat] indicate that addition of Si in Fe3Al increases the "1º"2 transitiontemperature while that of "2º("Fe) increases with up to about 12.5 at.% Si beyond which it levels off. Theinitial increase in ordering temperatures is consistent with the observation of [1977Nic1], and alsoconfirmed by [1987For]. A recent study of magnetic measurements [1986Tak] indicate that the ("Fe)º"2and "2º"1 transition temperatures vary non-monotonically with increasing Si-content as shown in Fig. 3.Minor adjustments have been made in Fig. 3 to comply with the accepted Al-Fe binary phase diagram, andalso by taking into account the results of [1982Cha] that the ("Fe)º"1 ordering temperature ofFe3(Al0.392Si0.608) is greater than 1050°C. Even though the effect of Si on the ordering induced phaseseparation around Fe3Al has not been investigated in detail, it is important to note that [1996Mor] observed("Fe)+"1 microstructure in an Fe-17Al-1Si(at.%) alloy in the temperature range of 400 to 600°C. It isexpected that the topology of the phase boundaries involving ordered ("1,"2) and disordered phases ("Fe)near Fe3Al will follow the general features of phase diagrams associated with multicritical points [1982All].Due to these reasons, several amendments are proposed in Fig. 3, shown by dotted lines, in the vicinity ofFe3Al.Even though, in general the nucleation and growth of "1 domain in "2 domain is easier than in ("Fe) matrix,the direct ("Fe)º"1 transformation in certain composition range has been attributed to the lowering ofatomic potential energy when Al atoms are substituted by Si atoms. This causes the formation of differenttypes of anti-phase boundaries and the corresponding changes in dislocation configuration leads to doubledissociation of superlattice dislocations [1982Cha]. Depending on the composition of the alloy, nucleationof the ordered phases can also take place directly from the melt. TEM and Mössbauer spectroscopy study[1983Gle] of an Fe-5.4Al-9.6Si(mass%) alloy revealed that the B2 type of ordering takes place directlyfrom the melt which subsequently undergoes D03 ordering. Also, [1969Pol] observed that the D03superlattice reflections persist up to the melting point in an alloy of Fe3Al+12 at.% Si. A similar conclusionwas also made by [1954Gar] who investigated the order-disorder transition, after quenching from differenttemperatures, in an Fe-9.7Si-5.5Al(mass%) alloy. By rapid quenching an Fe-5.4 mass% Al-9.6 mass% Sialloy, [1983Gle] observed that excess vacancies are introduced which occupy ordered sublattice positions,

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giving rise to a new crystallographic superstructure of the D03-type. Such type of vacancy-induced longrange ordering, from one crystal structure to another, has also been observed at other composition[1988Liu1].Mössbauer spectroscopy study of Fe73Al11Si16 (ALSIFER27) and Fe68Al22Si10 (ALSIFER32), by[1977Suw], revealed that excess diamagnetic atoms preferentially occupy particular D03 lattice sites whichis not observed from X-ray diffraction. They argued that powder methods used in X-ray diffraction may notrepresent the ordering reactions in the bulk materials. Also, Mössbauer study of Fe3Al1-xSix, for 0#x#1,indicates that 'order-annealing' treatment is accompanied by a separation of Fe3Al and Fe3Si types of localsurroundings [1983Sch]. However, this has only weak influence on the physical properties and thepredominant factor being the composition of the sample. [1987Dob] determined the atom locations inFe3-xAlxSi alloys with x=0.1, 0.2 and 0.3 having D03 structure, where Al atoms are confirmed to occupy theFe-sites.[1996Mor] studied the kinetics of ordering and phase separation in an Fe-17 at.% Al-1 at.% Si alloy in thetemperature range of 400 to 600°C, where they monitored the evolution of "+"1 microstructure. They foundthat partial substitution of Al by Si improves microstructural stability against coarsening, most probably dueto decrease diffusivity and a reduction in misfit strain.A theoretical study of ordering process in Fe0.5(Al1-xSix)0.5 [1999Mek] predicts an increase inorder-disorder temperature. Furthermore, they predicted that Si preferentially substitute Fe inFe0.5(Al1-xSix)0.5.

Pseudobinary Systems

[1931Fus] and [1934Fue] proposed a pseudobinary section Si-Fe4Al13 with a peritectic reactionL + Fe4Al13 º Fe2Al6Si3 at about 920°C and a eutectic reaction between (Si) and Fe2Al6Si3 at 850°C and32 mass% Si. However, later works failed to confirm the presence of such a pseudobinary section andconsequently it is disregarded.

Invariant Equilibria

At least nineteen invariant equilibria, in the solidification range of Al-Fe-Si alloys, have been reportedwhich are listed in Table 4. The assessed compositions of the liquid phase, after [1927Gwy, 1936Jae,1937Ura, 1940Tak, 1951Now, 1960Spe], for the ternary invariant reactions are listed in Table 4. [1940Tak]proposed nineteen ternary invariant reactions for the solidification of the Al-Fe-Si alloys. However, theyreported that some of these reactions take place in a very narrow range of temperature, thus, difficult toresolve by thermal analysis. For example, [1940Tak] proposed the following two reactions:L + g º "2 + FeAl2 at 1120°CL + FeAl2 º "2 + Fe2Al5 at 1115°C.These two reactions could not be distinguished clearly and a temperature interval of 5°C was assumed[1940Tak]. Also, they reported that it was difficult to distinguish FeAl2 from Fe2Al5 by etching. Instead ofthe above two reactions, the following invariant reaction is assumed in the present evaluation: L + g º "2 + Fe2Al5 at 1120°C.Ignoring the solubility of Si in FeAl2 and Fe2Al5, thermodynamic calculations [1998Kol, 1999Liu] givefollowing three reactions:g + Fe2Al5 º FeAl2, L (degenerate binary reaction)L + g º "2 + FeAl2 at 1125°C [1998Kol], at 1127°C [1999Liu]L + FeAl2 º "2 + Fe2Al5 at 1062°C [1998Kol], at 1073°C [1999Liu].Among these, the first reaction was not explicitly mentioned by the authors. Since the solubility of Si inFeAl2 and Fe2Al5 phases are not considered in thermodynamic modelling, the temperature of thethree-phase equilibrium g + Fe2Al5 + FeAl2 in the ternary is connected with the Si-content of g by a"generalized Raoult's law". In the Al-Fe system, the eutectic temperature of L º g + Fe2Al5 is very closelyabove the temperature of g + Fe2Al5 º FeAl2. For the three-phase equilibria going down from thesetemperatures into the ternary a "generalized Raoult's law" is valid, due to which the two three-phaseequilibria meet and form the above mentioned four-phase equilibrium. This meeting happens very near to

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the binary Al-Fe system. The amount of liquid participating in the four-phase equilibrium roughlycorresponds to the ratio of Si-solubility in g and liquid phases.[1981Riv] did not consider the participation of the L º "2 + Fe2Si binary invariant reaction in thesolidification process of the ternary alloys. Also, they did not consider Fe2Si to be a primary crystallizationproduct in the ternary regime. To alleviate these drawbacks, an invariant reaction with highest temperaturemust be assumed near the Fe-Si side. It is labelled as U1, and assumed to take place around 1150°C[1992Gho]:L + Fe2Si º "2 + FeSi In fact, the likelihood of U1 is also predicted in recent thermodynamic assessments of [1998Kol, 1999Liu].Thermodynamic modeling also confirmed the existence of following invariant reactions: P1, U3, U4, U5, P2,U7, U8, P5, U10, U11, U12 and E1. It should be noted that Fig. 4 represents only a partial reaction scheme. It considers participation of sixternary phases, J1, J2, J4, J5, J6 and J7, during solidification. The composition domain of liquid alloy whereJ3 is the primary crystallization product should be close to that of J2, but the available thermal analysis data[1940Tak] are insufficient to differentiate them. The reaction scheme does not account for the experimentalobservation of several three-phase fields, such as J2+J5+J6 at 600°C [1987Ste] and at 550°C [2001Kre],J2+J4+J6 at 550°C [2001Kre], J2+J4+J7 at 550°C [2001Kre]. These may originate from the invariantreactions L + J2 º J5 + J6 around 650°C [1952Arm, 1967Mun], L + J2 + J4 º J6 around 700°C [1927Gwy,1940Tak], and L + J7 º J3 + J4, respectively. However, to account for all experimentally observedthree-phase fields at 600 [1992Gho] and 550°C [2001Kre], including those involving J8 and J10, it isnecessary to introduce too many speculative invariant reactions. Therefore, no attempt was made to proposea complete reaction scheme. Nevertheless, further careful experiments are needed to establish the invariantreactions during solidification and also in the solid state.

Liquidus Surface

Figure 5 shows the liquidus surface of the Al-corner calculated by the dataset of [1999Liu], whichreproduces well those of [1927Gwy, 1943Phi, 1946Phi1]. The general form of the liquidus surface has beenconfirmed by other investigators [1933Nis, 1936Jae, 1937Ura, 1951Now, 1967Mun, 1987Gri1, 1988Zak].Nevertheless, some disagreement exists over the temperature contours. [1967Mun] reported that the coolingrate is an important factor. On the other hand, [1967Sun] using a variety of cooling rates confirmed the dataof [1927Gwy] and [1943Phi] and proposed that the nucleation is the decisive factor. [1977Igl] claimed amarked sensitivity of cooling rate not only on the temperature arrest, but also on the final product. In thisassessment, the data of [1927Gwy] and [1943Phi] are considered to be representative of normal equilibriumcondition and more complete compared to those reported by others [1933Nis, 1937Ura, 1951Now].Figure 6 shows the liquidus surface of the whole Al-Fe-Si system [1940Tak], depicting the melting groovesseparating 15 different areas of primary crystallization. Since the invariant reaction U1 has not beenexperimentally confirmed, part of the univariant lines formed by the "2, FeSi and Fe2Si crystallizationsurfaces have been shown dashed. Nevertheless, the U1 reaction complies with all the binary invariantreactions and experimental ternary phase diagrams. The calculated liquidus surfaces [1998Kol, 1999Liu]look similar, except in the Al-corner where they differ by several at.% in composition and up to 30°C intemperature compared to that of [1940Tak].Approximate isotherms at 50°C interval are superimposed in Fig. 6. In both Al-Fe and Fe-Si binary systems,depending on the alloy composition, either ("Fe) or "2 may be the primary crystallization product. In theternary system, as an approximation, the composition domains of ("Fe) and "2 as primary crystallizationproducts are delineated by the linear extrapolation between the composition limits of two binary edges. Thisis shown by a dashed line in Fig. 6. In the Fe-Si system, "1 is the primary crystallization product duringsolidification of alloys containing 27.5 to 32 at.% Si. However, the extension of this composition range intothe ternary system is not known. In the a comprehensive study of liquidus surface of the Al-corner, up to 70mass% Fe, by [1937Ura] agrees reasonably well with the results of [1940Tak]. The liquidus temperaturesof [1936Jae] are few tens of degrees higher than [1940Tak], and could be due to inadequate experimentalarrangements.

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Isothermal Sections

Figure 7 shows the isothermal section at 1000°C [1981Riv], drawn from the polythermal sections of[1940Tak]. At 1000°C, only one ternary phase, J1, is stable which is also expected from the reaction schemein Fig. 4. Also, in Fig. 7, the boundary between ("Fe) and "2 is shown by a dashed line which is a linearinterpolation between the composition limits of two binary edges. The extension of the binary intermediatephases into the ternary regime is given as approximate only. Figure 8 shows the isothermal section of theAl-corner at 640°C [1959Phi]. [1987Ste] reported the phase equilibria in a set of commercial Al-based alloyafter heat treating the as-cast samples for one month between 570 and 600°C. The heat treated state wasreferred to as “quasi-equilibrium” condition [1987Ste]. The phase equilibria of the Al-corner at 600°C isshown in Fig. 9, after [1987Pri] who amended the isothermal section reported by [1987Gri1] and [1987Ste].It is to be noted that the (Al)+J6 and (Al)+J6+(Si) phase fields were derived from the measurements onsamples annealed at 570°C. So the existence of these phase fields is consistent with the reaction scheme inFig. 4, giving the temperature for E1 as 573°C. Also, [1987Ste] reported that three ternary compounds"-FeAlSi (J5), $-FeAlSi (J6) and (-FeAlSi (J2), the details of which are given in Table 2, crystallize fromthe liquid. This is also consistent with the proposed reaction scheme in Fig. 4. During heat treatment of theas-cast samples, the Fe4Al13, J5 and (Si) phases react to form J6 phase, but this reaction does not go tocompletion [1987Ste]. Figure 10 shows the assessed isothermal section at 600°C. The Fe-corner involving the ordered phases istaken from [1986Miy], but at certain composition ranges the ordered phase regions are still doubtful, andthey are shown as dashed. The isothermal section at 600°C reported by [1981Zar] has undergone severalamendments. Previously reported [1992Gho] J1 and J9 phases are treated as one phase [2001Kre]. Thecomposition of J8 is accepted from [1996Yan]. Figure 11 shows the partial isothermal section at 550°C[2001Kre]. Even though temperature difference is only 50°C, there are important differences between Figs.10 and 11. For example, Fig. 10 shows the presence of (Al)+(Si)+J4 phase field which is not accounted forby the reaction scheme, while Fig. 11 shows the presence of (Al)+(Si)+J6 phase field which is consistentwith the reaction scheme in Fig. 4. Figure 10 shows the presence of J10+Fe2Al5+Fe4Al13 phase field, whileFig. 11 shows the presence of J1/J9+Fe2Al5+Fe4Al13 phase field. In Fig. 11, several phase boundariesinvolving J8 are uncertain. [2001Kre] reported that the tie-triangles involving J8 will depend on itscomposition, which was not determined. As a results, some of the phase boundaries in J8 are shown dotted. Figure 12 shows the partial isothermal section at 500°C proposed by [1984Don] in which the phaseboundaries have shifted to the right, compared to [1943Phi, 1946Phi1, 1946Phi2], in order to account forthe observation of various phases as well as the amount of Si in solid solution in the (Al) matrix inindustrially pure Al. Figures 13, 14, 15, 16 show the isothermal sections of the Fe-corner at 700, 650, 550 and 450°C,respectively, after [1986Miy] who studied ternary alloys, containing up to 40 at.% solute atoms (Al+Si), bymeans of transmission electron microscopy. These figures depict the states of different kinds of order internary Fe-rich alloys as a function of composition and temperature. [1986Miy] reported two types of phaseseparation "1(D03)+"2(B2) and ("Fe)+"1(D03) in the ternary alloys connecting Fe-10 to 14 at.% Si withFe-20 to 25 at.% Al and also near Fe-30 at.% Si alloy. The morphology of the <100> modulated structurein Fe-Si and Al-Fe-Si alloys differs from that of the Al-Fe system [1986Miy]. X-ray diffraction data andTEM observations of [1971Gle] concerning various order-disorder reaction in the ternary alloysqualitatively agree with those of [1986Miy]

Temperature – Composition Sections

Figures 17, 18 and 19 show polythermal sections of the ternary system at 0.7 mass% Fe [1949Cru, 1959Phi],at 4.0 mass% Fe [1959Phi] and at 8.0 mass% Si [1959Phi], respectively. There are no published data for thesolidus projection of the entire system, even though a number of polythermal projections are available[1927Gwy, 1932Nis, 1933Nis, 1940Tak, 1946Phi1]. The solidus projection of the Fe-corner was reported[1968Lih], but their results differ substantially along the Al-Fe binary edge, so they are not accepted here.Since Al-rich solid solutions can dissolve only about 0.052 mass% Fe, the solidus of the Al-corner[1961Phi] of the Al-Fe-Si system is shown in Fig. 20 on an enlarged scale.

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Thermodynamics

Thermodynamic properties of ternary alloys have been investigated a number of times by measuring theheat of formation of solid alloys [1937Koe, 1937Oel], activity measurements in liquid alloys [1969Bed,1970Mit, 1973Nag, 1973Per, 1980Sud, 1984Ber, 1985Cao, 1989Bon], and the standard heat of formationof ternary intermetallics [1997Vyb, 2000Li1, 2000Li2]. The energetics of chemical ordering in the ternarysystem has been described by [1991Fuk] and [1994Koz]. Besides, thermodynamic modeling of the ternarysystem has also been carried out by the CALculation of PHase Diagram (CALPHAD) method [1994Ang,1995Gue3, 1998Kol, 1999Liu], where the Gibbs energies of the relevant phases are described by simpleanalytical functions.[1969Bed] determined the activity coefficients at several constant mole fraction ratios (xSi/xFe) at 1627°C.The Al activities in the temperature range of 800 to 1100°C were reported by [1973Nag], and at 900°C by[1973Per]. [1980Sud] reported Al activity in an Fe-1 mass% Al-1 mass% Si alloy at 1485 and 1546°C.Further experiments were carried out by [1984Ber] and [1989Bon]. The latter authors measured thechemical potential of Al in alloys containing up to 11.8 at.% Fe and 23.7 at.% Si by the concentration cellmethod in the temperature range of 577 to 1027°C. The activities of Al show a negative deviation from idealbehavior. The results of [1984Ber] also show a similar trend.The heat of mixing of solid alloys was measured by pouring liquid Al-Si alloy and liquid Fe into a watercalorimeter [1937Koe,1937Oel]. However, the state of equilibrium in these experiments is uncertain[1999Liu]. The standard heat of formation of ternary intermetallics, except J7, has been determined bysolution calorimetry by [1997Vyb], [2000Li1] and [2000Li2]. [1997Vyb] used 99.99% Al, 99.9% Fe and99.99% Si to prepare single phase J5 and J6 samples by annealing cast ingots either at 550°C (J5) or at600°C (J6) for 1 month. They used an aluminum bath at 1070°C for solution calorimetry. Li et al [2000Li1,2000Li2] used 99.99% Al, 99.999% Fe and 99.999% Si, and prepared ingots by levitation melting followedby annealing, the conditions of which were varied to obtain single phase alloys of J5, J10, J1 and J9[2000Li1], and J6, J2, J3, J8 and J4 [2000Li2]. Unlike [1997Vyb], Li et al used an aluminum bath at a lowertemperature of 800°C for solution calorimetry. There are differences between the results of [1997Vyb] and[2000Li1, 2000Li2]. For example, [1997Vyb] reported that the standard heat of formation of J5(Fe19.2Al71.2Si9.6) and J6 (Fe15.4Al69.2Si15.4) are –34.3±2 and –24.5±2 kJ/atom, respectively. Thecorresponding values reported by Li et al are –24.44±1.39 kJ/mol for J5 at Fe18Al72Si10 [2000Li1] and–20.209±0.926 kJ/mol for J6 at Fe15Al70Si15 [2000Li2]. Even though the J5 and J6 compositions of[1997Vyb] and [2000Li1, 2000Li2] are not identical, large differences in heat of formation are unexpected.Apparently, Li et al [2000Li1, 2000Li2] were unaware of the results of [1997Vyb], and they did not discussthis discrepancy. Nevertheless, it is not clear if a higher bath temperature (causing oxidation) and relativelyimpure starting materials used by [1997Vyb] compared to Li et al have contributed to more negative heatof formation.[1994Ang] determined the enthalpy of fusion of FeAl3Si2 (J4) and Fe5Al8Si7 (J7). [1949Cru] reported calculated solubility isotherms of Fe and Si in solid (Al). They suggested the formationof a ternary compound Fe2Al7Si which is close to the J5 phase at low Si content. On the other hand theircalculation seems to suggest the ternary phase FeAl5Si which is close to the J6 phase [1981Riv]. Calculationof the liquidus surface from a purely thermodynamic approach [1946Phi2] seems to produce good resultnear the binary edges. However, their approach can neither predict the composition of the precipitatingphase nor calculate the solidus curves. [1994Ang] employed the CALPHAD technique and calculated two vertical sections corresponding toxAl/xSi=3/1 and at xSi=0.85. [1995Gue3] calculated two partial isothermal sections at 600 and 900°C, and avertical section at xSi=0.78 by the CALPHAD method. They considered only two ternary phases: FeAl3Si2(J4) and Fe2Al9Si2 (J6). [1991Fuk, 1994Koz] performed a theoretical analysis of phase separation involving "Fe, "2 and "1 phases.The free energy of ternary alloys is evaluated statistically using a pair-wise interaction up to second nearestneighbor. Both chemical and magnetic interactions based on Bragg-Williams-Gorsky model were used. Thecalculated phase diagrams are found to be consistent with the experimental ones.

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[1998Kol] and [1999Liu] carried out detailed thermodynamic assessments of the ternary system by theCALPHAD method. According to our classification, [1998Kol] considered six ternary phases J1, J2, J3, J4,J5 and J6, whereas [1999Liu] considered seven ternary phases: J1, J2, J3, J4, J5, J6, and J7, called J1, (, J23,*, ", $, J, respectively. [1999Liu] argued that J2 and J3 have very similar Fe contents, and wondered, if theyare the same phase with a small homogeneity range. This view was also accepted by [2002Rag]. However,as summarized in Table 2, J2 and J3 have different crystal structures. [1999Liu] computed the liquidussurface, isothermal sections at 600 and 1000°C, and vertical sections at 1.3, 2, 5, 10% Fe and 2% Si (mass).

Notes on Materials Properties and Applications

[1951Oga1, 1951Oga2, 1983Sch] reported the ferromagnetic behavior of Fe3Al-Fe3Si alloys. [1968Aru1,1968Aru2, 1970Aru] reported that the occupation of ordered sites by all three Al, Fe and Si atomsaccompanied with a minimum in electrical resistivity at Fe75Al18Si7 and Fe6(Al,Si). [1996Szy] reportedthat dissolved Al in FeSi2(r) increases its magnetic susceptibility, and both FeSi and FeSi2(r) exhibit VanVleck paramagnetism even at very low temperature (up to 4.2 K). [1996Fri] and [1998Dit] studied themetal-insulator transition in Al doped FeSi. [1998Dit] reported lattice constant, thermoelectric effect, Halleffect, electrical conductivity, magnetic susceptibility, specific heat and magnetoresistance in FeSi1-xAlx,with 0 # x # 0.08. All these properties confirm a metal to insulator transition of FeSi, which is otherwisea Kondo insulator. [1999Oht] has reported that doping of FeSi2(r) with 3 at.% Al improves itsthermoelectric figure of merit. The magnetic properties of ternary alloys have been discussed in detail by[1986Tak] and [1988Dor].[1993Sch] investigated the plastic deformation of single-crystal Al20Fe75Si5 alloy as a function oftemperature. The critical resolved shear stress exhibits a non-monotonic behavior with a maximum around530°C. The non-monotonic behavior was correlated with the temperature-dependent dislocation mobilityrather than a decrease in D03 long-range order parameter. [1996Cho, 2001Cho] reported the microstructure,hardness and tensile properties of Al-5Fe-16Si(mass%) alloy, processed by powder metallurgy up to 520°C.[1948Jen] demonstrated a relationship between the constitutional diagram and the susceptibility to crackingof the Al-Fe-Si alloys. A key factor in determining the corrosion behavior of Al-rich alloys is the Fe/Si ratio.Low Fe/Si ratio in ternary alloys exhibit better corrosion resistance in both industrial and marineenvironment [2000Bha].

Miscellaneous

In recent years, the solidification of Al-rich ternary alloys has been investigated rather extensively[1983Per, 1991Don, 1991Lan, 1995Bel, 1995Gue3, 1996All, 1997All, 1997Sto, 1997Can, 1999Cho,1999Tay, 2000Dut, 2001Hsu, 2001Sha, 2002Mer]. [1983Per] discussed the effect of metastable liquidmiscibility gaps, metastable eutectic and metastable peritectic on the rapid solidification processing andalloy design. Addition of up to 0.11 mass% Si in a Al-0.5 mass% Si alloy is reported to favor the formationof the metastable phase FeAl6 [1978Suz].[1995Bel] proposed a non-equilibrium solidification method to analyze the cast microstructure of ternaryalloys. This method utilizes equilibrium phase diagram, but assumes that the peritectic reactions aresuppressed and the eutectic reactions occur according to the equilibrium phase diagram. Cantor andco-workers [1996All, 1997All, 1997Can] have discussed the role of heterogeneous nucleation on the phaseselection and solidification.[1997Sto] studied the effect of cooling rate and solidification velocity on the microstructure selection ofAl-3.5 mass% Fe-(1 to 8.5) mass% Si alloys by wedge chill casting and Bridgman directional solidificationtechniques. In the latter case, the front growth velocity was in the range of 0.01 to 2 mm/s under atemperature gradient of 15°C/mm. Also, at front velocities greater than 1 mm/s, the primary intermetallicswere suppressed. The results of Al-3.5 mass%Fe-8.5 mass% Si were summarized in terms of a kineticallybased solidification microstructure selection diagram. [1999Tay] applied Scheil equation to predict thedefect-onset (porosity) during solidification of Al-rich alloys as a function of Fe and Si contents. They foundthat a defect-free casting can be obtained if the solidification proceeds directly to the invariant reaction E1(LºJ6+(Al)+(Si)), whereas poor casting may result when the solidification proceeds via the (Al)-J6 eutectic

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valley. The critical Fe-content at which the porosity is minimized is a function of Si-content in the alloy.[2001Sha] also carried out Bridgman directional solidification of a model 6xxx alloy (Al-0.3 mass% Fe-0.6mass% Si-0.8 mass% Mg), and obtained solidification front velocity in the range of 5 to 120 mm/min. Theyobserved two ternary phases, "-FeAlSi (J5) and $-FeAlSi (J6), of which the latter is metastable. At low frontvelocity, such as 30 to 60 mm/min, $-FeAlSi dominate the microstructure, while at high front velocity, suchas 120 mm/min, $-FeAlSi dominates the phase selection. Figure 21 shows the surface of secondary crystallization of the Al-corner after [1943Phi]. It should be notedthat the data relate to slowly-cooled alloys in a non-equilibrium state.Since both the Al-Fe and Fe-Si binary systems form (-loops, a ternary (-loop is expected. [1931Wev]reported the coordinates of the phase boundaries of the ternary (-loop which are listed in Table 5.[1960Voz] reported the effect of impurities on the solid solubility of Al alloys by means of electricalresistivity. [1972Ere] studied the dissolution kinetics of Fe in Al-Si melts at 700, 750 and 800°C, thekinetics of which was correlated with the formation of various intermediate phases.[2000Sri] reported synthesis of bulk ternary intermetallics using elemental powder mixture byself-propagating high temperature synthesis. They used cold compacted powder mixtures that were heatedto 650°C in a vacuum furnace. Both stable (J2, J5 and J6) and metastable phases were obtained in thisprocess. They also reported hardness of the intermetallics.[1998Akd] proposed that the value of activity coefficient of Al in "-(Fe,Al,Si) alloys has a strong influenceon the formation and growth kinetics of interfacial diffusion layer. [1999Oht] has discussed the sinteringmechanism of Al-Fe-Si alloys, particularly the role of liquid phase, in the context of fabricating an Al-dopedFeSi2(r) phase. [2001Jha] has discussed the diffusion path of Al in ternary bcc alloys.

References

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[1923Wet] Wetzel, E., “Advances in Aluminium Research” (in German), Die Metallboerse, 13,737-738 (1923) (Equi. Diagram, Experimental, 6)

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[1937Oel] Oelsen, W., “The Heats of Formation of Binary and Ternary Alloys and Their Importancein Metallurgical Reactions” (in German), Z. Electrochem., 43, 530-535 (1937)(Experimental, Thermodyn., 15)

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[1941Pan] Panseri, C., Guastalla, B., “Investigations on the Permanent Modification of EutecticAluminium-Silicon Alloys. I.-Influence of Titanium Additions as the third Components”,Allumino, 10(5), 202-227 (1941) (Equi. Diagram, Experimental, Review, 161)

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[1943Phi] Phillips, H.W.L., Varley, P.C., “Constitution of Alloys of Aluminium with Magnesium,Silicon and Iron”, J. Inst. Met., 69, 317-350 (1943) (Equi. Diagram, Experimental, #, *, 11)

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[1951Hol] Holik, L., Nowotny, H., Thury, W., “Investigation of the Microstructure in the Al-Corner ofthe System Aluminium-Iron-Silicon” (in German), Berg- u. Huettenmn. Monatsh. Hochsch.Leoben, 96, 181-184 (1951) (Equi. Diagram, Experimental, #, *, 12)

[1951Now] Nowotny, H., Komerek, K., Kromer, J., “An Investigation of the Ternary System:Aluminium-Iron-Silicon” (in German), Berg- u. Huettenmn. Monatsh. Hochsch. Loeben, 96,161-169 (1951) (Crys. Structure, Equi. Diagram, Experimental, *, 31)

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[1951Oga2] Ogawa, S., Matsuzaki, Y., “Study on the Superlattice of Ternary Alloys by X-rays”, Sci.Rep. Res. Inst. Tohoku Univ., 3A, 50-54 (1951) (Crys. Structure, Experimental, *, 9)

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[1951Pra2] Pratt, J.N., Raynor, G.V., “The Intermetallic Compounds in the Alloys of Aluminium andSilicon with Chromium, Manganese, Iron, Cobalt and Nickel”, J. Inst. Met., 79, 211-232(1951) (Crys. Structure, Equi. Diagram, Experimental, #, *, 32)

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[1951Sat] Sato, H., Yamamoto, H., “The Behaviours of Fe-Al, Fe-Si and Fe-Al-Si Alloys Consideredfrom the Standpoint of Ferromagnetic Supperlattice”, J. Phys. Soc. Jpn., 6, 65-66 (1951)(Experimental, *, 2)

[1952Arm] Armand, M., “On the Phases in the Ternary System Aluminium-Iron-Silicon” (in French),Comt. Rend. Acad. Sci. Paris, 235, 1506-1508 (1952) (Crys. Structure, Experimental, *, 9)

[1952Han] Hanemann, H., Schrader, A., Ternary Alloys of Aluminium (in German), Verlag: Stahleisen,Duesseldorf, 109-115 (1952) (Equi. Diagram, Review, #, 12)

[1953Rob] Robson, K., Black, P.J., “An X-ray Examination of an "-(Al-Fe-Si) Ternary Compound”,Philos. Mag., 44, 1392-1397 (1953) (Crys. Structure, Experimental, *, 10)

[1954Gar] Garrod, R.I., Hogan, L.M., “The Superlattice in Sendust”, Acta Metall., 2, 887-888 (1954)(Crys. Structure, Experimental, *, 5)

[1954Spi] Spiegelberg, A.P.W., Danielsson, S.L.A., Astroem, H., “The Crystal Structure of SomePhases Occurring in Alloys of Aluminium, Iron and Silicon and Their Relationship to otherPhases”, Acta Crystallogr., 7, 634 (1954) (Crys. Structure, Experimental, *, 4)

[1955Arm] Armand, M., “Liquation and Equilibrium Diagram: Applications to the Diagram ofAluminium-Iron-Silicon Alloys” (in French), Congress International de l'Aluminium, Paris,1954, Revue de l'Aluminium, 1, 305-327 (1955) (Crys. Structure, Experimental, *, 9)

[1955Bla] Black, P.J., “Brillouin Zones of Some Intermetallic Compounds”, Philos. Mag., 46, 401-409(1955) (Crys. Structure, Experimental, *, 23)

[1955Obi] Obinata, I., Komatsu, N., “On the Phases Occuring in Alloys of Aluminium with Iron andSilicon” (in Japanese), Nippon Kinzoku Gakkaishi, 19, 197-201 (1955) (Crys. Structure,Experimental, 30)

[1956Spe] Sperry, P.R., “The Intermetallic Phases in 2024 Aluminum Alloys”, Trans. ASM, 48,904-918 (1956) (Experimental, 11)

[1959Phi] Phillips, H.W.L., Annoted Equilibrium Diagrams of Some Al Alloy Systems, Monograph,Inst. of Met., London, (25), 57-65 (1959) (Equi. Diagram, Review, #, *, 18)

[1960Lee] Lee, J.R., “Liquidus-Solidus Relations in the System Iron-Aluminum”, J. Iron Steel Inst.Met., 194, 222-224 (1960) (Equi. Diagram, Experimental, 5)

[1960Spe] Spengler, H., “The Importance of Research on Eutectics and its Application to TernaryEutectic Aluminium Alloys” (in German), Metall, 14, 201-206 (1960) (Experimental)

[1960Voz] Vozdvizhenskiy, V.M., “The Effect on the Saturation of Solid Solution in Some Al Alloys”(in Russian), Izv. Vyss. Uchebn. Zaved., Tsvetn. Metall., (5), 116-120 (1960) (Equi.Diagram, Experimental, 19)

372


MSIT®

Al–Fe–Si

[1961Phi] Phillips, H.W.L., “Al-Fe-Si”, in “Equilibrium Diagrams of Aluminium Alloy Systems”, TheAluminium Develop. Assoc., London, 91-96 (1961) (Equi. Diagram, Experimental, #, *)

[1961Sab] Sabirzyanev, A.V., Shumilov, M.A., Gel´d, P.V. Ozhogikhina, G.V., “Solubility of Al in"-Leoboite”, Phys. Met. Metallogr., 12(5), 81-87 (1961), translated from Fiz. Met.Metalloved., 12, 714-721 (1961) (Crys. Structure, Experimental, 14)

[1964Lai] Lainer, D.A., Kurakin, A.K., “Mechanism of the Influence of Silicon in Aluminium on theReaction Diffusion of Iron”, Phys. Met. Metallogr., 18, 134-137 (1964), translated from Fiz.Met. Metalloved., 18, 145-148 (1964) (Crys. Structure, Experimental, 13)

[1965Sab] Sabirzyanev, A.V., Shumilov, M.A., “The Solubility of Al and P in Constituents of High-SiFerrosilicon” (in Russian), Tr. Ural'sk Politekh. Inst., 144, 35-40 (1965) (Experimental, 14)

[1965Skr] Skripova, E.A., Letun, G.M., “The Solubility of Al in "-Leboite” (in Russian), Tr. Ural'skPolitekh. Inst., 144, 67-70 (1965) (Crys. Structure, Experimental, 4)

[1967Coo] Cooper, M., “The Crystal Structure of the Ternary Alloys S-AlFeSi”, Acta Crystallogr., 23,1106-1107 (1967) (Crys. Structure, Experimental, *, 5)

[1967Mun] Munson, D., “A Clarification of the Phases Occuring in Aluminium-RichAluminium-Iron-Silicon Alloys with Particular Reference to the Ternary Phase "-AlFeSi”,J. Inst . Met., 95, 217-219 (1967) (Crys. Structure, Equi. Diagram, Experimental, *, 12)

[1967Sun] Sun, C.Y., Mondolfo, L.F., “A Clarification of the Phases Occuring in Al-Rich Al-Fe-SiAlloys”, J. Inst. Met., 95, 384 (1967) (Crys. Structure, Experimental, *, 2)

[1968Aru1] Arutyunyan, S.V., Selissky, Ya.P., “The Question of Superstructure in Fe-Si-Al Alloys” (inRussian), Izv. Akad. Nauk. Arm. SSR, Fizika, 3, 8-11 (1968) (Crys. Structure,Experimental, 5)

[1968Aru2] Arutyunyan, S.V., “Some Features of Atomic Ordering in Ternary Fe-Si-Al Alloys” (inRussian), Izv. Akad. Nauk Arm. SSR, Fizika, 3, 294-297 (1968) (Crys. Structure,Experimental, 2)

[1968Dri] Drits, M.E., Kadaner, E.S., Turkina, N.I., “The System Al-Fe-Si” (in Russian), in“Diagrammy Sostoyaniya Metallich. Sistem”, Nauka, Moscow, XIV, 109 (1968) (Equi.Diagram, Review, 1)

[1968Lih] Lihl, F., Burger, R., Sturm, F., Ebel, H., “Constitution of Fe-rich Ternary Al-Fe-Si Alloys”,Arch. Eisenhuettenwes., 39, 877-880 (1968) (Equi. Diagram, Experimental, *, 22)

[1968Sab1] Sabirzyanev, A.V., Gel´d, V.P., “Some Features of the Peritectoid Transformation in$-Leboite (FeSi2) Alloys Alloyed with Al, Ca and P” (in Russian), Tr. Ural'sk Politekh.Inst., 167, 75-80 (1968) (Experimental, 6)

[1968Sab2] Sabirzyanev, A.V., Gel´d, V.P., “Nature of Solid Solutions of Aluminium and Phosphorusin Iron Monosilicide” (in Russian), Izv. Vyss. Uchebn. Zaved., Chern. Metall., 11, 21-26(1968) (Experimental, 3)

[1969Bed] Bedon., P., Ansara, I., Desre, P., “Isothermal Sections at 1900 K of theSilver-Aluminium-Iron-Silicon and Silver-Aluminium-Nickel-Silicon Metallic Systems;Activity of Aluminium in Molten Aluminium-Iron-Silver-Silicon andAluminium-Nickel-Silver Alloys” (in French), Mem. Sci. Rev. Metall., 66, 907-913 (1969)(Experimental, Thermodyn., 5)

[1969Pan] Panday, P.K., Schubert, K., “Structure Studies in Some Alloys T-B3-B4 (T = Mn, Fe, Co, Ir,Ni, Pd; B4 = Si, Ge)” (in German), J. Less-Common Met., 18, 175-202 (1969) (Crys.Structure, Experimental, *, 32)

[1969Pol] Polishchuk, V.E., Selissky, YA.P., “High-Temperature Study of the Structure and ElectricalProperties of the Fe-Si-Al System” (in Russian), Ukrain. Fiz. Zhur., 14, 1722-1724 (1969)(Equi. Diagram, Experimental, #, *, 9)

[1970Aru] Arutyunyan, S.V., “Transition from Atomic Ordering to Disordering in Fe3(Al,Si) AlloysRelated to the Formation of the K-Effect” (in Russian), Izv. Akad. Nauk Arm. SSR, Ser. Tekh.Nauk, 32, 36-42 (1970) (Experimental, 4)

373


MSIT®

Al–Fe–Si

[1970Mit] Mitani, H., Nagai, H., Ohtani, T., “Dry Refining of Aluminium. IV. Activity Measurementsof the Ternary Liquid Al-Fe-Si System by the EMF Method” (in Japanese), Nippon KinzokuGakkaishi, 34, 165-170 (1970) (Experimental, Thermodyn., 16)

[1971Gle] Glezer, A.M., Molotilov, B.V., Polishchuk, V.Ye., Selissky, Ya.P., “X-ray and ElectronMicroscopic Analysis of the Fine Structure of Ordering High-Fe-Al-Si Alloys”, Phys. Met.Metallogr., 32(4), 39-47 (1971) (Experimental, 19)

[1972Ere] Eremenko, V.N., Natanzon, Ya.V., Ryabov, V.R., Dzykovich, I.Ya., “Interaction of Al-SiMelts with Steel” (in Russian), Liteinoe Proizvod., (2), 21-22 (1972) (Experimental)

[1973Kat] Katsnel´son, A.A., Polishchuk, V.Ye., “Energy Characteristics of Atomic Ordering inAlloys of Iron with Aluminium and Silicon”, Phys. Met. Metallogr., 36(2), 86-90 (1972)(Equi. Diagram, Experimental, #, *, 10)

[1973Kow] Kowatschewa, R., Dafinowa, R., Kamenowa, Z., Momtschilov, E., “MetallographicDetermination of Intermetallic Compounds in Aluminium Alloys”, Metallography, 10,131-143 (1973) (Crys. Structure, Experimental, 9)

[1973Nag] Nagai, H., Mitani, H., “Activity Measurements of the Ternary Liquid Al-Si-Fe System bythe EMF Method”, Tran. Jpn. Inst. Met., 14, 130-134 (1973) (Experimental, Thermodyn., 9)

[1973Per] Perkins, J., Desre, P., “Determination of Activities in the Al-Fe-Si System by a EMFMethod” (in French), Rev. Int. Hautes Temp. Refract., 10, 79-84 (1973) (Experimental,Thermodyn., 13)

[1974Mur] Murav´eve, A.A., German, N.V., Zarechnyuk, O.S., Gladyshevskii, E.I., “TernaryCompounds of the Fe-Al-Si System” (in Russian), Proc. 2nd All-Union Conf. on Crys.Chem. Intermet. Compounds, L'vov, October, 35-36 (1974) (Crys. Structure, Experimental,*)

[1975Bar] Barlock, J.G., Mondolfo, L.F., “Structure of Some Aluminum-Iron-Magnesium-SiliconAlloys”, Z. Metallkd., 66, 605-611 (1975) (Crys. Structure, Equi. Diagram, Experimental, *,7)

[1977Cor] Corby, R.N., Black, P.J., “The Structure of "-AlFeSi by Anomalous Dispersion Method”,Acta Crystallogr. B: Struct. Crystallogr. Crys. Chem., 33B, 3468-3475 (1977) (Crys.Structure, Experimental, *, 18)

[1977Hoi] Hoeier, R., Lohne, O., Moertvedt, S.T., “AlFeSi-Particles in an Al-Mg-Si-Fe Alloy”, Scand.J. Metall., 6, 36-37 (1977) (Crys. Structure, Experimental, *, 3)

[1977Igl] Iglessis, J., Frantz, C., Gantois, M., “Conditions for the Formation of the Iron Phases inCommercial Purity Aluminium-Silicon Alloys” (in French), Mem. Sci. Rev. Metall., 74,237-242 (1977) (Experimental, *, 14)

[1977Nic1] Niculescu, V., Raj, K., Burch, T., Budnick, J.J., “Hyperfine Interactions and StructuralDisorder of Fe2Si1-xAlx Alloys”, J. Phys. F, Met. Phys., 7, L73-76 (1977) (Experimental, 7)

[1977Nic2] Niculescu, V., Budnick, J.J., “Limits of Solubility, Magnetic Properties and ElectronConcentration in Fe3-xTxSi System”, Solid State Commun., 24, 631-634 (1977) (Theory, 17)

[1977Sim] Simensen, C.J., Vellasamy, R., “Determination of Phases Present in Cast Material of anAl-0.5 wt.% Fe-0.2 wt.% Si Alloy”, Z. Metallkd., 68, 428-431 (1977) (Crys. Structure,Experimental, 10)

[1977Suw] Suwalski, J., Kisynska, K., Piekoszewski, J., “Distribution of Fe Atoms in OrderedFe1-x(Al,Si)x”, Proc. Int. Conf. Mössbauer Spectroscopy, Barb, D., Tarina, D. (Eds.),Docum. Office, Central Inst. Phys., Bucharest, Romania, 125-126 (1977) (Theory, 2)

[1978Suz] Suzuki, H., Kanno, M., Tanabe, H., Itoi, K., “The Effect of Si or Mg Addition on theMetastable to Stable Phase Changes in an Al-0.5% Fe Alloy” (in Japanese), J. Jpn. Inst.Light Met., 28, 558-565 (1978) (Crys. Structure, Experimental, 7)

[1978Xu] Xu, W.-C., Su, X.-J., “An Investigation on the Structure of Fe-Si-Al Alloy” (in Chinese),Acta Phys. Sin., 27, 576-582 (1978) (Crys. Structure, Experimental, *, 9)

[1979Bur] Burch, T.J., Raj, K., Jena, P., Budnick, J.I., Niculescu, V., Muir, W.B., “Hyperfine-FieldDistribution in Fe3Si1-xAlx Alloys and a Theoretical Interpretation”, Phys. Rev. B: SolidState, 19B, 2933-2938 (1979) (Experimental, Theory, 17)

374


MSIT®

Al–Fe–Si

[1979Cow] Cowdery, J.S., Kayser, F.X., “Lattice Parameters of Ferromagnetic D03-StructuredIron-Aluminium-Silicon Alloys”, Mater. Res. Bull., 14, 91-99 (1979) (Crys. Structure,Experimental, *, 24)

[1979Mor] Mora, R., “The Determination of the Al-Fe-Si Phase in Homogenized Aluminium Alloy6063” (in Spanish), Rev. Metall., 15, 91-95 (1979) (Crys. Structure, Experimental, *, 15)

[1980Sud] Sudavsova, V.S., Batalin, G.I., “Aluminium Activity in Liquid Iron Alloys” (in Russian),Ukrain. Khim. Zhur., 46, 268-270 (1980) (Experimental, Thermodyn., 8)

[1981Riv] Rivlin, V.G., Raynor, G.V., “Phase Equilibria in Iron Ternary Alloys 4: Critical Evaluationof Constitution of Aluminium-Iron-Silicon System”, Int. Met. Rev., 26, 133-152 (1981)(Equi. Diagram, Review, #, *, 56)

[1981Wat] Watanabe, H., Sato, E., “Phase Diagram in Aluminium Alloys” (in Japanese), J. Jpn. Inst.Light Met., 31, 64-79 (1981) (Equi. Diagram, Review, #, *, 22)

[1981Zar] Zarechnyuk, O.S., German, N.V., Yanson, T.I., Rykhal, R.M., Murav'eva, A.A., “SomePhase Diagrams of Aluminium with Transition Metals, Rare Earth Metals and Silicon” (inRussian), in “Fazovje Ravnovesija v Metallicheskych Splavach”, Nauka, Moscow, 69-71(1981) (Crys. Structure, Equi. Diagram, Experimental, #, *, 5)

[1982All] Allen, S.M., Cahn, J.W., “Phase Diagram Features Associated with Multicritical Points inAlloy Systems”, Bull. Alloy Phase Diagrams, 3(3), 287-295 (1982) (Theory, 25)

[1982Cha] Chang, Y.J., “An Electron Microscopic Investigation of Order-Disorder Transformation ina Fe-Si-Al (SENDUST) Alloy and its Dislocation Configurations”, Acta Metall., 30,1185-1192 (1982) (Crys. Structure, Experimental, 17)

[1982Kub] Kubaschewski, O., “Iron-Aluminium”, “Iron-Silicon”, in “Iron-Binary Phase Diagrams”,Springer Verlag, Berlin, 5-9 and 136-139 (1982) (Equi. Diagram, Review, #, *, 26, 23)

[1982Miy] Miyazaki, T., Tsuzuki, T., Kozakai, T., Fujimoto, Y., “Phase Separation of Fe-Si-AlOrdering Alloys” (in Japanese), Nippon Kinzoku Gakkai-Si, 46, 1111-1119 (1982) (Crys.Structure, Experimental, 37)

[1982Wes] Westgren, H., “Formation of Intermetallic Compounds During DC Casting of CommercialPurity Al-Fe-Si Alloy”, Z. Metallkd., 73, 361-368 (1982) (Crys. Structure, Experimental,24)

[1983Gle] Glezer, A.M., Molotilov, B.V., Prokoshin, A.F., Sosnin, V.V., “Structural Features of aSENDUST (Fe-Si-Al) Alloy Obtained by Quenching from the Melt. I. The Study of AtomicOrdering Properties”, Phys. Met. Metallogr., 56(4), 110-117 (1983), translated from Fiz.Met. Metalloved., 56(4), 750-757 (1983) (Crys. Structure, Experimental, *, 12)

[1983Per] Perepezko, J.H., Boettinger, J.W., “Use of Metastable Phase Diagrams in RapidSolidification”, Proc. Mater. Soc. Symp., Alloy Phase Diagrams, 19, 223-240 (1983)(Review, Theory, 52)

[1983Sch] Schneeweiss, O., Zemcik, T., Zak, T., Mager, S., “Atomic Structure and MagneticProperties of the Pseudobinary Alloys Fe3(Al,Si)”, Phys. Status Solidi A, 79A, 125-129(1983) (Experimental, 10)

[1984Ber] Berecz, E., Bader, I., Weberner, Kovacs, E., Hovath, J., Szina, G., “ThermodynamicExamination of Aluminium Alloys by the Electrochemical Method” (in Hungarian),Banyasz. Kohasz. Lapok, Kohasz, 117, 413-417 (1984) (Experimental, Thermodyn., 10)

[1984Don] Dons, A.L., “AlFeSi-Particles in Commercial Pure Aluminium”, Z. Metallkd., 75, 170-174(1984) (Equi. Diagram, Experimental, #, *, 10)

[1984Mat] Matsumura, S., Sonobe, A, Oki, K., Eguchi, T., “Ordering with Phase Separation in anFe-Al-Si Alloy”, in “Phase Transformations in Solids”, Proc. Conf. Mater. Res. Soc.,Elsevier, Amsterdam, 21, 269-274 (1984) (Crys. Structure, Experimental, 12)

[1985Cao] Cao, R., Li, G., Wu, X., “Some Thermodynamic Properties in Process of Thermal Reductionof Magnesium with High Aluminium Alloy” (in Chinese), Acta Metall. Sin., 21, A471-A476(1985) (Experimental, Thermodyn., 9)

[1985Don1] Dons, A.L., “Superstructure in "-Al(MnFeCrSi)”, Z. Metallkd., 76, 151-153 (1985) (Crys.Structure, Experimental, *, 11)

375


MSIT®

Al–Fe–Si

[1985Don2] Dons, A.L., “AlFeSi-Particles in Industrially Cast Aluminium Alloys”, Z. Metallkd., 76,609-612 (1985) (Experimental, 14)

[1985Gri] Griger, A., Stefaniay, V., Turmezey, T., “Analysis of Ternary Al-Fe-Si Phases on HighPurity Base”, Proc.: 6th Int. Symp. High Purity Mater. Sci. Techn., Supplement, Dresden,GDR, 6-10 May, 187-188 (1985) (Experimental)

[1985Liu] Lui, P., Thorvaldsson, L., Dunlop, G.L., “The Formation of Intermetallic Compoundsduring Solidification of Dilute Al-Fe-Si Alloys”, Ultramicroscopy, 17, 178 (1985) (Crys.Structure, Experimental)

[1985Riv] Rivlin, V.G., “Assessment of Phase Equilibria in Ternary Alloys of Iron”, J. Less-CommonMet., 114, 111-121 (1985) (Equi. Diagram, Review, #, *, 4)

[1985Suz] Suzuki, H., Arai, K., Shiga, M., Nakamura, Y., “Mössbauer Effect of Al-Fe-Si IntermetallicCompounds”, Metall. Trans. A, 16A, 1937-1942 (1985) (Experimental, 22)

[1986Len] Lendvai, A., “Phase Diagram of the Al-Fe System up to 45 mass% Iron”, J. Mater. Sci. Lett.,5, 1219-1220 (1986) (Equi. Diagram, Experimental, 7)

[1986Dun] Dunlap, R.A., Dini, K., “Amorphization of Rapidly Quenched QuasicrystallineAl-Transition Metal Alloys by the Addition of Si”, J. Mater. Res., 1, 415-419 (1986) (Crys.Structure, Experimental, 19)

[1986Liu1] Liu, P., Dunlop, G.L., “Constituent Formed during Solidification of Al-Fe-Si Alloys”, Proc.Conf. Aluminium Alloys: Their Physical and Mechanical Properties, I, Chalottesville,Virginia, USA, 15-20 (1986) (Crys. Structure, Experimental, *, 20)

[1986Liu2] Lui, P., Thorvaldsson, L., Dunlop, G.L., “Formation of Intermetallic Compounds duringSolidification of Dilute Al-Fe-Si Alloys”, Mater. Sci. Technol., 2, 1009-1018 (1986) (Crys.Structure, Experimental, *, 26)

[1986Miy] Miyazaki, T., Kozaki, T., Tsuzuki, T., “Phase Decomposition of Fe-Si-Al Ordered Alloys”,J. Mater. Sci., 21, 2557-2564 (1986) (Equi. Diagram, Experimental, #, *, 26)

[1986Tak] Takahashi, M., “Magnetic Properties of Iron-Silicon-Aluminium Alloy Single Crystals” (inJapanese), Kotai Butsuri, 21, 259-273 (1986) (Experimental, 48)

[1987Ben] Bendersky, L.A., Biancaniello, F.S., Schaefer, R.J., “Amorphous Phase Formation inAl70Si17Fe13 Alloys”, J. Mater. Res., 2, 427-430 (1987) (Experimental, 21)

[1987Cha] Chandrasekaran, M., Liu, Y.P., Vincent, R., Staniek, G., “On a Metastable RhombohedralAl-Fe-Si Intermetallic Phase”, Proc. Electron Microsc. Analysis Group Meeting,Manchester, Sept. (1987), 63-65 (1988) (Crys. Structure, Experimental, 5)

[1987Czi] Cziraki, A., Fogarassy, B., Oszko, A., Szabo, I., Teravaginov, A., Reibold, M., “Effect ofHeat Treatment on the Microstructure of Cast Al-Fe-Si Alloys”, Mater. Sci. Forum, 13-14,343-350 (1987) (Crys. Structure, Experimental, 5)

[1987Dob] Dobrzynski, L., Giebultowicz, T., Kopcewicz, M., Piotrowski, M., Szymanski, K., “Neutronand Mössbauer Studies of Fe3-xAlxSi Alloys”, Phys. Status Solidi A, 101A, 567-575 (1987)(Crys. Structure, Experimental, 24)

[1987For] Fortnum, R.T., Mikkola, D.E., “Effects of Molybdenum, Titanium and Silicon Additions onthe D03 Reversible B2 Transition-Temperature for Alloys near Fe3Al”, Mater. Sci. Eng., 91,223-231 (1987) (Crys. Structure, Experimental, 37)

[1987Gri1] Griger, A., Lendrai, A., Stefaniay, V., Turmezey, T., “On the Phase Diagrams of the Al-Feand Al-Fe-Si Systems”, Mater. Sci. Forum, 13/14, 331-336 (1987) (Equi. Diagram,Experimental, 9)

[1987Gri2] Griger, A., “Powder Data for the "H Intermetallic Phases with Slight Variation inComposition in the System Al-Fe-Si”, Powder Diffr., 2, 31-35 (1987) (Crys. Structure,Experimental, *, 21)

[1987Liu] Liu, P., Dunlop, G.L., “Determination of the Crystal Symmetry of Two Al-Fe-Si Phases byConvergent-Beam Electron Diffraction”, J. Appl. Crystallogr., 20, 425-427 (1987) (Crys.Structure, Experimental, 13)

[1987Nag] Nagy, S., Homonnay, Z., Vertes, A., Murgas, L., “Mössbauer Investigation of Iron inAluminium. II. Al-Fe-Si Samples”, Acta Metall., 35, 741-746 (1987) (Experimental, 2)

376


MSIT®

Al–Fe–Si

[1987Pri] Prince, A., “Comment on Intermetallic Phases in the Al-side of the AlFeSi-Alloy System”,J. Mater. Sci. Lett., 6, 1364 (1987) (Equi. Diagram, Theory, #, 1)

[1987Skj1] Skjerpe, P., “Intermetallic Phases Formed during DC-Casting of an Al-0.25 wt.% Fe-0.13wt.% Si Alloy”, Metall. Trans. A, 18A, 189-200 (1987) (Crys. Structure, Experimental, 35)

[1987Skj2] Skjerpe, P., Gjonnes, J., “Solidification Structure and Primary Al-Fe-Si Particles inDirect-Chilled-Cast Aluminum Alloys”, Ultramicroscopy, 22, 239-250 (1987) (Crys.Structure, Experimental, 21)

[1987Skj3] Skjerpe, P., “An Electron Microscopy Study on the Phase Al3Fe”, J. Microsc., 148, 33-50(1987) (Crys. Structure, Experimental, Theory, 12)

[1987Ste] Stefaniay, V., Griger, A., Turmezey, T., “Intermetallic Phases in the Aluminum-Side Cornerof the AlFeSi-Alloy System”, J. Mater. Sci., 22, 539-546 (1987) (Crys. Structure, Equi.Diagram, Experimental, #, *, 13)

[1987Tur] Turmezey, T., “AlFe and AlFeSi Intermetallic Phases in Aluminum Alloys”, Mater. Sci.Forum, 13/14, 121-132 (1987) (Crys. Structure, Experimental, 12)

[1988Ben1] Bendersky, L., “Rapidly Solidified Al-Fe-Si Alloys”, Mater. Sci. Eng., 98, 213-216 (1988)(Crys. Structure, Experimental, 9)

[1988Ben2] Bendersky, L.A., McAlisetr, A.J., Biancaniello, F.S., “Phase Transformation duringAnnealing of Rapidly Solidified Al-Rich Al-Fe-Si Alloys”, Metall. Trans. A, 19A,2893-2900 (1988) (Crys. Structure, Experimental, 29)

[1988Cha] Chandrasekaran, M., Lin, Y.P., Vincent, R., Staniek, G., “The Structure and Stability ofSome Intermetallic Phases in Rapidly Solidified Al-Fe”, Scr. Metall., 22, 797-802 (1988)(Crys. Structure, Experimental, 9)

[1988Dor] Dorofeyeva, Ye.A., Sasnin, Y.V., Stolokotniy, V.L., “Cross-Relaxation of MagneticPermeability in Alloy FeSiAl”, Phys. Met. Metallogr., 65(3), 172-174 (1988)(Experimental, 2).

[1988Liu1] Liu, P., Dunlop, G.L., “Long-range Ordering of Vacancies of BCC "-AlFeSi”, J. Mater.Sci., 23, 1419-1424 (1988) (Crys. Structure, Experimental, 20)

[1988Liu2] Liu, P., Dunlop, G.L., “Crystallographic Orientation Relationships for Al-Fe and Al-Fe-SiPrecipitates in Aluminum”, Acta Metall., 36, 1481-1489 (1988) (Crys. Structure,Experimental, 20)

[1988Ray] Raynor, G.V., Rivlin, V.G., “Al-Fe-Si”, in “Phase Equilibria in Iron Ternary Alloys”,122-139 (1988) (Equi. Diagram, 39)

[1988Zak] Zakharov, A.M., Gul´man, I.T., Arnol´d, A.A., Matsenko, Yu.A., “Phase Diagram of theAluminium-Silicon-Iron System in the Concentration Range of 10-14% Si and 0-3% Fe”,Russ. Metall., (3), 177-180 (1988) (Equi. Diagram, Experimental, #, *, 8)

[1989Bon] Bonnet, M., Rogez, J., Castanet, R., “EMF Investigation of Al-Si, Al-Fe-Si and Al-Ni-SiLiquid Alloys“, Thermochim. Acta, 155, 39-56 (1989) (Experimental, Thermodyn., 15)

[1989Tib] Tibballs, J.E., “Al-Si Substitution in Al(FeMn)Si Phases”, Mater. Sci. Forum, (1989) (23) [1989Ger1] German, N.V., Bel`skii, V.K., Yanson, T.I., Zarechnyuk, O.S., “Crystal Structure of the

Compound Fe1.7Al4Si”, Sov. Phys. Crystallogr., 34(3), 437-438 (1989) (Crys. Structure,Experimental, 5)

[1989Ger2] German, N.V., Zavodnik, V.E., Yanson, T.I., Zarechnyuk, O.S., “Crystal Structure ofFeAl2Si”, Sov. Phys. Crystallogr., 34(3), 439-440 (1989) (Crys. Structure, Experimental, 5)

[1991Don] Dons, A.L., “Simulation of Solidification a Short Cut to a Better Phase DiadramAl-Mg-Fe-Si Alloys”, Z. Metallkd., 82(9), 684-688 (1991) (Calculation, Equi. Diagram,Experimental, Thermodyn., 17)

[1991Fuk] Fukaya, M., Miyazaki, T., Kozakai, T., “Phase Diagrams Calculated for Fe-rich Fe-Si-Coand Fe-Si-Al Ordering Systems”, J. Mater. Sci., 26(2), 5420-5426 (1991) (Calculation,Equi. Diagram, 42)

[1991Lan] Langsrud, Y., “The Use of Phase Diagrams for Calculating Solidification Paths”, “UserAspects of Phase Diagrams”, Proc. Conf., Hayes, F.H. (Ed.), The Inst. of Metals, 1991,90-100 (Publ. 1991) (Theory, 7)

377


MSIT®

Al–Fe–Si

[1992Gho] Ghosh, G., “Aluminium-Iron-Silicon”, MSIT Ternary Evaluation Program, in MSITWorkplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,Stuttgart; Document ID: 10.14596.1.20, (1992) (Crys. Structure, Equi. Diagram,Assessment, 134)

[1992Zak] Zakharov, A.M., Guldin, I.T., Arnold, A.A., Matsenko, Yu.A., “Phase Equilibria inMulticomponent Aluminum Systems with Copper, Iron, Silicon, Manganese and Titanium”,Metalloved. Obrab. Tsv. Splavov, RAN. Inst. Metallurgii. M, 6-17 (1992) (Experimental,Equi. Diagram, 14)

[1993Car] Carpenter, G.J.C., Le Page, Y., “Revised Cell Data for the $-FeSiAl Phase in AluminumAlloys”, Scr. Metall. Mater., 28, 733-736 (1993) (Crys. Structure, Experimental, 6)

[1993Sch] Schroeer, W., Hartig, C., Mecking, H., “Plasticity of D03-ordered Fe-Al and Fe-Al-SiSingle-Crystals”, Z. Metallkd., 84(5), 294-300 (1993) (Equi. Diagram, Experimental, 30)

[1994Ang] Anglezio, J.C., Servant, C., Ansara, I., “Contribution to the Experimental andThermodynamic Assessment of the Al-Ca-Fe-Si System - I. Al-Ca-Fe, Al-Ca-Si, Al-Fe-Siand Ca-Fe-Si Systems”, Calphad, 18(3), 273-309 (1994) (Calculation, Equi. Diagram,Thermodyn., 71)

[1994Koz] Kozakai, T., Miyazaki, T., “Experimental and Theoretical Investigations on Phase Diagramsof Fe Base Ternary Ordering Alloys”, ISIJ Int., 34(5), 373-383 (1994) (Calculation, Equi.Diagram, Magn. Prop., 18)

[1994Mur] Murali, S., Guru Row, T.N., Sastry, D.H., Raman, K.S., Murthy, K.S.S., “Crystal Structureof $-FeSiAl5 and (Be-Fe)-BeSiFe2Al8 Phases”, Scr. Metall. Mater., 31(3), 267-271 (1994)(Experimental, 13)

[1994Rag] Raghavan, V., “The Al-Fe-Si System”, J. Phase Equilib., 15(4), 414-416 (1994) (Equi.Diagram, Review, 27)

[1994Rom] Romming, Chr., Hansen, V., Gjonnes, J., “Crystal Structure Of Beta-Al4.5FeSi”, ActaCrystallogr., Sect. B: Struct. Crystallogr. Crys. Chem., B50(3), 307-312 (1994) (Crys.Structure, Experimental, 10)

[1995Bel] Belov, N.A., “Analysis of Nonequilibrium Solidification of Subeutectic Sillumines UsingMulticomponent Phase Diagrams”, Russ. Metall. (Engl. Transl.), (1), 41-47 (1995) (Equi.Diagram, Experimental, 5)

[1995Gue1] Gueneau, C., “FeAl3Si2”, Acta Crystallogr., Sect. C: Cryst. Struct. Commun., C51, 177-179(1995) (Crys. Structure, Experimental, 9)

[1995Gue2] Gueneau, C., Servant, C., “Fe2Al3Si3”, Acta Crystallogr., Sect. C: Cryst. Struct. Commun.,C51, 2461-2464 (1995) (Crys. Structure, Experimental, 8)

[1995Gue3] Gueneau, C., Servant, C., Ansara, I., “Experimental and Thermodynamic Assessments ofSubstitutions in the AlFeSi, FeMnSi, FeSiZr and AlCaFeSi Systems”, “Appl. Thermodyn.Synth. Procee. Mater.”, Proc. Symp., Nash, P., Sundman, B. (Eds.), The Minerals, Metalsand Materials Society, Warrendale, Pa, 303-317 (1995) (Expermental, Theory, 19)

[1996All] Allen, C.M., O’Reilly, K.A.Q., Cantor, B., Evans, P.V., “Nucleation of Phases in Al-Fe-SiAlloys”, Mater. Sci. Forum, 217-222, 679-684 (1996) (Calculation, Equi. Diagram, 14)

[1996Cho] Choi, Y., Ra, H., “Microstructure of Gas Atomized Al-Fe-Si Alloy Powders” (in Korean),J. Korean Inst. Met., 34(2), 230-235 (1996) (Experimental, 11)

[1996Fri] Friemelt, K., Ditusa, J.F., Bucher, E., Aeppli, G., “Coulomb Interactions in Al Doped FeSiat Low Temperatures”, Ann. Phys., Leipzig, 5(2), 175-183 (1996) (Crys. Structure,Experimental, 25)

[1996Mor] Morris, D.G., Gunther, S., “Order-Disorder Changes in Fe3Al Based Alloys and theDevelopment of an Iron-Base "-"`` Superalloy”, Acta Mater., 44(7), 2847-2859 (1996)(Crys. Structure, Equi. Diagram, Experimental, 23)

[1996Mul] Mulazimoglu, M.H., Zaluska, A., Gruzleski, J.E., Parray, F., “Electron Microscopy Study ofAl-Fe-Si Intermetallics in 6021 Aluminum Alloys”, Metall. Mater. Trans. A, 27A, 929-936(1996) (Crys. Structure, Experimental, 48)

378


MSIT®

Al–Fe–Si

[1996Mur] Murali, S., Raman, K.S., Murthy, K.S.S., “Al-7Si-0.3Mg Cast Alloy: Formation and CrystalStructure of $-FeSiAl5 and (Be-Fe)-BeSiFe2Al8 Phases”, Mater. Sci. Forum, 217-222,207-212 (1996) (Crys. Structure, Experimental, 8)

[1996Szy] Szymanski, K., Baas, J., Dobrzynski, L., Satula, D., “Magnetic and Mössbauer Investigationof FeSi2-xAlx”, Physica B (Amsterdam), 225, 111-120 (1996) (Crys. Structure,Experimental, 20)

[1996Yan] Yanson, T.I., Manyako, M.B., Bodak, O.I., German, N.V., Zarechnyuk, O.S., Cerny, R.,Pacheko, J.V., Yvon, K., “Triclinic Fe3Al2Si3 and Orthorhombic Fe3Al2Si4 with NewStructure Types”, Acta Crystallogr., Sect. C: Cryst. Struct. Commun., C52, 2964-2967(1996) (Crys. Structure, Experimental, 15)

[1997All] Allen, C.M., O`Reilly, K.A.Q., Cantor, B., Evans, P.V., “Heterogeneous Nucleation ofSolidification of Equilibrium and Metastable Phases in Melt-Spun Al-Fe-Si Alloys”, Mater.Sci. Eng. A, A226-A228, 784-788 (1997) (Experimental, Phys. Prop., 10)

[1997Can] Cantor, B., “Impurity Effects on Heterogenous Nucleation”, Mater. Sci. Eng. A,A226-A228, 151-156 (1997) (Crys. Structure, Experimental, 38)

[1997Sto] Stone, I.C., Jones, H., “Effect of Cooling Rate and Front Velosity on SolidificationMicrostructure Selection in Al-3.5 wt.% Fe-0 to 8.5 wt.% Si Alloys”, Mater. Sci. Eng. A,A226-A228, 33-37 (1997) (Equi. Diagram, Experimental, 10)

[1997Vyb] Vybornov, M., Rogl, P., Sommer, F., “The Thermodynamic Stability and Solid SolutionBehavior of the Phases J5-Fe2Al7.4Si and J6-Fe2Al9Si2”, J. Alloys Compd., 247, 154-157(1997) (Crys. Structure, Equi. Diagram, Experimental, Review, 7)

[1998Akd] Akdeniz, M.V., Mekhrabon, A.O., “The Effect of Substitutional Impurities on the Evolutionof Fe-Al Diffusion Layer”, Acta Mater., 46(4), 1185-1192 (1998) (Calculation,Thermodyn., 55)

[1998Dit] Ditusa, J.F., Friemelt, K., Bucher, E., Aeppli, G., Ramirez, A.P., “Heavy FermionMetal-Kondo Insulator Transition in FeSi1-xAlx”, Phys. Rev. B, B58(16), 10288-10301(1998) (Crys. Structure, Experimental, 62)

[1998Kol] Kolby, P., “System Al-Fe-Si”, in “COST 507, Thermochemical Database for Light MetalAlloys”, Vol. 2, Ansara, I., Dinsdale, A.T., Rand, M.H. (Eds), Office for official publicationsof the European Communities, Luxembourg, 319-321 (1998) (Assessment, Thermodyn.)

[1999Cho] Choi, Y.S., Lee, L.S., Kim, W.T., Ra, H.Y., “Solidification Behavior of Al-Si-Fe Alloys andPhase Transformation of Metastable Intermetallic Compound by Heat Treatment”, J. Mater.Sci., 34(9), 2163-2168 (1999) (Equi. Diagram, Experimental, 14)

[1999Liu] Liu, Z.-K., Chang, A., “Thermodynamic Assessment of the Al-Fe-Si System”, Metall.Mater. Trans. A., 30A(7), 1081-1095 (1999) (Calculation, Thermodyn., 56)

[1999Mek] Mekhrabov, A.O., Akdeniz, M.V., “Effect of Ternary Alloying Elements Addition onAtomic Ordering Characteristics of Fe-Al Intermetallics”, Acta Mater., 47(7), 2067-2075(1999) (Calculation, Theory, Thermodyn., 63)

[1999Oht] Ohta, Y., Miura, S., Mishima, Y., “Thermoelectric Semiconductor Iron Disilicides Producedby Sintering Elemental Powders”, Intermetallics, 7, 1203-1210 (1999) (Equi. Diagram,Experimental, Thermal Conduct., 19)

[1999Tay] Taylor, J.A., Schaffer, G.B., St. John, D.H., “The Role of Iron in the Formation of Porosityin Al-Si-Cu-Based Casting Alloys: Part II. A Phase-Diagram Approach”, Metall. Mater.Trans. A, 30A, 1651-1655 (1999) (Calculation, Crys. Structure, Experimental, 12)

[2000Bha] Bhattamishra, A.K., Chattoraj, I., Basu, D.K., De, P.K., “Study on the Influence of the Si/FeRatio on the Corrosion Behavior of Some Al-Fe-Si Alloys”, Z. Metallkd., 91(5), 393-396(2000) (Corrosion, Experimental, 23)

[2000Dut] Dutta, B., Rettnmayr, M., “Effect of Coolig Rate on the Solidification Behavior of Al-Fe-SiAlloys”, Mater. Sci. Eng. A, A283, 218-224 (2000) (Equi. Diagram, Experimental, 23)

[2000Li1] Li, Y., Ochin, P., Quivy, A., Telolahy, P., Legendre, B., “Enthalpy of Formation of Al-Fe-SiAlloys (J5, J10, J1, J9)”, J. Alloys Compd., 298, 198-202 (2000) (Experimental,Thermodyn., 20)

379


MSIT®

Al–Fe–Si

[2000Li2] Li, Y., Legendre, B., “Enthalpy of Formation of Al-Fe-Si Alloys II (J6, J2, J3, J8, J4)”,J. Alloys Compd., 302, 187-191 (2000) (Experimental, Thermodyn., 21)

[2000Sri] Sritharan, T., Murali, S., Hing, P., “Synthesis of Aluminium-Iron-Silicon Intermetallics byReaction of Elemental Powders”, Mater. Sci. Eng. A, A286, 209-217 (2000) (Crys.Structure, Experimental, 18)

[2000Zhe] Zheng, J.G., Vincent, R., Steeds, J.W., “Crystal Structure of an Orthorhombic Phase inbeta-(Al-Fe-Si) Precipitates Determined by Convergent-Beam Electron Diffraction”,Philos. Mag. A, A80(2), 493-500 (2000) (Crys. Structure, Experimental, 11)

[2001Cho] Cho, H.S., Kim, K.S., Jeong, H.G., Yamagata, H., “Microstructure and MechanicalProperties of Extruded Rapidly Solidified Al-16Si-5Fe Based Alloys”, Key Eng. Mater.,189-191, 479-483 (2001) (Experimental, Mechan. Prop., 5)

[2001Hsu] Hsu, G., O´Reilly, K.A.Q., Cantor, B., Hamerton, R., “Non-Equilibrium Reactions in 6xxxSeries Al Alloys”, Mater. Sci. Eng. A, A304-A306, 119-124 (2001) (Equi. Diagram,Experimental, 14)

[2001Jha] Jha, R., Haworth, C.W., Argent, B.B., “The Formation of Diffusian Coatings on SomeLow-Alloy Steels and Their High Temperature Oxidation Behavior: Part 1 DiffusionCoatings”, Calphad, 25(4), 651-665 (2001) (Calculation, Equi. Diagram, 9)

[2001Kre] Krendelsberger N., “Constitution of the Systems Aluminium-Manganese-Silicon,Aluminium-Iron-Silicon, und Aluminium-Iron-Manganese-Silicon”, Tezisy Inst. Phys.Chem. Univ., Vienna, 2001 (Crys. Structure, Equi. Diagram, Experimental, #, *, 83)

[2001Sha] Sha, G., O´Reilly, K., Cantor, B., Worth, J., Hamerton, R., “Growth Related MetastablePhase Selection in a 6xxx Series Wrought Al Alloy”, Mater. Sci. Eng. A, A304-A306,612-616 (2001) (Crys. Structure, Equi. Diagram, Experimental, 9)

[2002Mer] Meredith, M.W., Worth, J., Hamerton, R.G., “Intermetallic Phase Selection DuringSolidification of Al-Fe-Si(-Mg) Alloys”, Mater. Sci. Forum, 396-402, 107-112 (2002)(Equi. Diagram, Experimental, 9)

[2002Rag] Raghavan, V., “Al-Fe-Si (Aluminium-Iron-Silicon)”, J. Phase Equilib., 25(4), 107-112(2002) (Equi. Diagram, Review, 24)

[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSITWorkplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 58)

[2003Luk] Lukas, H.L., “Al-Si (Aluminum-Silicon)”, MSIT Binary Evaluation Program, in MSITWorkplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,Stuttgart; to be published, (2003) (Assessment, Equi. Diagram, Crys. Structure, 29)

Table 1: Chronological Survey of Ternary Phases in the Al-Fe-Si System

Author Phase Designation Composition (mass%)CommentsFe Al Si

[1927Gwy] P, $, *, . - - - Ternary alloys up to ~20%Fe and 30%Si (mass%) were studied. The .-phase reported to be solid solution of Fe, Al and Si.

[1928Dix] "(Fe-Si) $(Fe-Si)

30.027.0

62.068.0

8.015.0

Ternary alloys up to 41%Fe and 29%Si(mass%) were studied using pure Al(99.95%).Annealing: 1-5 weeks at 560°C. These two crystal species were reported to be ternary solid solutions rather than ternary compounds. Reported to form a part-section with Fe4Al13 and $(Fe-Si).

[1931Fin] "(Fe-Si) $(Fe-Si)

30.3 27.3

61.457.7

8.315.0

Alloys and heat treatments were same as [1928Dix]. They assumed "(Fe-Si) was a solid solution of Si in Fe4Al13.

[1931Fus] Fe2Al6Si3 31.3 45.2 23.5 Fe2Al6Si3 formed by a peritectic reaction.

380


MSIT®

Al–Fe–Si

[1932Nis],[1933Nis]

Fe2Al3Si2 P

44.9-

32.5-

22.6 -

Fe2Al3Si2 was reported around the composition Al-32Fe-30Si (mass%). The P-phase was not studied further.

[1935Bos] Fe2Al6Si3 - - - [1936Jae] FeAl4Si2

Hexagonal Orthorhombic Triclinic

27.2---

47.6---

25.2---

XRD, goniometric and dilatometric measurements were carried out in ternary alloys up to 40%Fe and 30% Si (mass%). The chemical compositions of the hexagonal (a=836, c=1458 pm), orthorhombic (a=609, b=996, c=374 pm) and triclinic (a=688, b=593, c=432 pm, "= 104.75°, $=130.67°, (=68.4°) phases were not given. FeAl4Si2 has tetragonal structure (a=615, c=947 pm).

[1937Ser] FeAlnSi n = 4 n = 5 FeAl4Si2

29.125.625.4

56.361.649.1

14.612.825.5

Microscopic and XRD were carried out in alloys up to 10%Fe and 25%Si (mass%). The densities of FeAl5Si and FeAl4Si2 were reported to be 3.35 and 3.30 g cm-3, respectively. FeAl4Si2 was found to have cubic crystal structure.

[1937Ura] $ (

--

--

--

According to these authors $ and ( are formed by peritectic reaction, they have no definite composition, and are solid solutions.

[1940Tak] K1:Fe3Al3Si2K2:Fe6Al12Si5K3:Fe5Al9Si5K4:FeAl3Si2K5:Fe6Al15Si5K6:FeAl4Si

55.0 41.9 42.2 28.9 38.1 29.1

26.6 40.5 36.7 41.9 46.0 56.3

18.4 17.6 21.1 29.2 15.9 14.6

These authors reported six ternary phases (K1 to K6) formed by peritectic reactions.

[1943Phi] "(Fe-Si) $(Fe-Si)

- -

- -

- -

They investigated ternary alloys up to 12 mass% Fe and 6 mass% Si.

[1950Phr] c-FeAlSi m-FeAlSi

t-FeAlSi

31.9 27.2-27.8-

62.5 59.3-58.2-

5.6 13.5-14.0-

Alloys up to 42%Fe and 30%Si(mass%) were studied. c-FeAlSi has cubic (a=1254.83 pm), m-FeAlSi has monoclinic (a=b=612.23, c=4148.36 pm, $=91°) and t-FeAlSi has tetragonal (a=612.23, c=947.91 pm) structure.

[1951Pra2] "(Fe-Si)

$-(Fe-Si)

32.1-32.726.7-27.3

59.5-57.059.5-57.8

8.4-10.3 13.8-14.9

Chemical analysis and XRD were carried out on extracted crystals. The crystal structure of "(Fe-Si) was reported to be the same as Fe4Al13 and $(Fe-Si) represents a distinct ternary compound.

[1951Now] "(Fe-Si) $(Fe-Si) ((Fe-Si) *(Fe-Si)

30.6 27.2 28.9 -

59.1 59.1 41.9 -

10.3 13.7 29.2 -

150 ternary alloys up to 45%Fe and 30% Si (mass%) were investigated by thermoanalytical, microscopic and XRD methods. Homogeneity ranges of these phases were reported to be small. Approximate stoichiometries of "(Fe-Si), $(Fe-Si), ((Fe-Si) can be represented as Fe1.5Al6Si, FeAl4.5Si, Fe0.5Al1.5Si, respectively. The latter has tetragonal structure (a = 495.0, c = 707.0 pm).


381


MSIT®

Al–Fe–Si

[1952Arm] [1955Arm]

"1 "2 "3

27.3 29.2 35.3

65.7 59.5 51.9

7.0 11.3 12.8

Alloys up to 20%Fe and 50% Si (mass%) were studied. Microscopic, XRD and density measurements were performed to characterize the phases in as-cast alloys. The crystal structures of "1, "2 and "3 were reported to be cubic (a = 1254.83 pm), hexagonal (a = 496, c = 702.11 pm) or orthorhombic (a = 4360, b = 4960, c = 7080 pm) and cubic (a = 1603.23 pm), respectively. The densities were 3.50, 3.58 and 3.65 g@cm-3, respectively.

[1953Rob] "-FeAlSi 32.5 58.8 8.7 Single crystals of "-FeAlSi, prepared by [1951Pra1] and [1951Pra2] were studied by X-ray diffraction. The crystal structure and density were reported to be hexagonal (with P63/mmc symmetry and a = 1230, c = 2620 pm) and 3.62±0.02 g@cm-3 respectively.

[1954Spi] c-FeAlSi t-FeAlSi m-FeAlSi

- - -

-- -

- - -

The crystal structures of c-FeAlSi, t-FeAlSi and m-FeAlSi were reported to be cubic (a = 1254.23 pm), tetragonal (a = 612.23, c = 948.94 pm) and monoclinic (a = b = 612.23, c = 4148.36 pm, $ = 91°), respectively. They correspond to "(Fe-Si), $(Fe-Si) of [1943Phi] and ( of [1927Gwy], respectively.

[1955Bla] Fe2Al9Si2 27.2 59.1 13.7 XRD was carried out on the extracted crystals of [1951Pra1]. The crystal structure and density were reported to be tetragonal (with 4/m symmetry and a = 618±6, c = 4250±50 pm) and 3.50±0.1 g@cm-3, respectively.

[1955Obi] "(Fe-Si)

$(Fe-Si)

30.2-32.823.4-25.8

58.1-60.0 57.6-58.5

11.2-7.219.0-15.7

"(Fe-Si) was obtained in Al-5Fe-(3 to 7)Si (mass%) which were water quenched after annealing at 615 to 620°C for 1 h, and $(Fe-Si) was obtained in Al-4Fe-(9 to 13)Si (mass%) alloys which were f/c cooled after the same heat treatment. These crystals were extracted from alloys after subjecting to different heat treatments and were studied by XRD. The powder patterns obtained from these two phases were almost the same as c-FeAlSi and m-FeAlSi of [1950Phr]. The lattice parameters of "(Fe-Si) and $(Fe-Si) were a=1254.8 pm; and a = b = 612.2, c = 4148.4 pm, and $ = 91°, respectively.

[1956Spe] "(Mn, Fe)AlSi - - - Found in wrought commercial 2024 alloy.[1964Lai] FeAl5Si - - - Formed in an Al-1.5 mass% Si alloy plated with

Fe and annealed at 500°C. The ternary phase was identified by X-ray and electron diffraction techniques.


382


MSIT®

Al–Fe–Si

[1967Coo] "-FeAlSi 31.9 61.7 6.4 XRD study of these crystals yielded cubic structure with a=1256 pm, 138 atoms/unit cell and Im3 symmetry. The composition of the crystals was close to Fe5Al20Si2 and the density was ~3.59±0.06 g@cm-3.

[1967Mun] "-CrFeAlSi "-FeAlSi $-FeAlSi (-FeAlSi

*-FeAlSi

- - - 33.0-38.0-

- - - 54.0-43.5 -

- - - 13.0-18.5 -

Alloys containing up to 22 mass% (Fe+Si) were cooled at 0.75°C/min. The phases were analyzed by X-ray and electron diffraction. The crystal structures of "-CrFeAlSi, "-FeAlSi and (-FeAlSi were reported to be cubic (a=1250 to 1270 pm), hexagonal (a=1230, c=2620 pm) and C-face-centered monoclinic (a=1780±10, b=1025±5, c=890±5 pm, $=132°), resp. The "cubic" (a=1603 pm) pattern of "3 of [1955Arm] was indexed on the basis of this monoclinic cell. *-FeAlSi was reported to be the same as "2 of [1952Arm].

[1967Sun] "1(FeAlSi) "2(Fe2Al8Si)

"3(FeAl3Si)

$(FeAl5Si)

*(FeAl4Si2)

31.1 30.0-33.0 34.0-35.2 25.5-26.5 25.0-26.0

60.8 62.6-56.0 50.4-47.7 62.4-58.9 49,0-47.0

8.1 7.4-11.0 15.6-17.1 12.1-14.626.0-27.0

50 different ternary and quaternary alloys were analyzed by chemical and X-ray diffraction. The "1 crystals were reported to contain 1.05 mass% Mn. The crystal structures of "1 and "2 were reported to be cubic (a = 1250±10 pm) and hexagonal, respectively.

[1969Pan] FeAl3Si2 28.9 41.9 29.2 The alloy was annealed at 800°C for 14 h and water quenched, and was analyzed by XRD. The crystal structure was reported to be tetragonal (a = 607, c = 950 pm) of PdGa5-type,

[1973Kow] Fe2Al9Si2 - - - Found in Al-11.17Si-0.4Fe-0.49Mg-9.8Si and Al-0.1Fe-0.4Mg-7.5Si-0.1Ti (mass%) alloys. The extracted crystals were analyzed by XRD and microprobe analysis. The composition of the precipitate as given by the authors does not add up to 100.

[1974Mur], [1981Zar]

A: Fe15Al57-47Si28-38

B: Fe22Al40Si38 C: Fe32Al38Si30 D: Fe36Al36Si28 E: Fe40Al40Si20 F: Fe25Al60Si15 G: Fe25Al50Si25 K: Fe22Al63-52Si15-36

L: Fe15Al70Si15 M: Fe17Al72Si11

26.5-27.5 36.4 48.9 53.3 57.7 40.5 40.6 36.7-36.6 26.6 29.7

40.0-48.6 32.0 28.1 25.8 27.8 39.1 47.1 50.7-41.7 60.0 60.7

33.5-24.9 31.6 23.0 20.9 14.5 20.4 12.3 12.6-21.7 13.4 9.6

The crystal structures of Fe25Al50Si25, Fe25Al60Si15 and Fe22Al63-52Si15-36 were reported to be orthorhombic (a = 768, b = 1530, c = 1600 pm), hexagonal (a = 752.6, c = 763.2 pm) and monoclinic (a = 420, b = 760, c = 1533 pm, $ = 89°), respectively. The crystal structures of other phases were not reported. The A-phase has hexagonal crystal structure with lattice parameters varying from a = 630±0.5, c = 941±0.7 pm at Fe15Al57Si28 to a = 612±0.5, c = 953±0.7 pm at Fe15Al47Si38. In the as-cast samples, the F-phase has hexagonal structure, but its structure is different after annealing at 600°C.


383


MSIT®

Al–Fe–Si

[1975Bar] FeAl5Si Fe2Al8Si

25.0 31.0

62.0 61.0

13.0 8.0

These two phases were found in Al-Fe-Mn-Mg-Si alloys. The crystal structures of FeAl5Si and Fe2Al8Si were reported to be monoclinic (a = b = 612, c = 4150 pm, $ = 91°) and hexagonal (with P63/mmc symmetry and a = 1230, c = 2630 pm), respectively.

[1977Cor] "-(FeAlSi) 32.5 58.8 8.7 The extracted crystal of [1951Pra2] were analyzed by X-ray diffraction using Mo-K", Fe-K" and Cu-K" radiations. The crystal structure was reported to be hexagonal (a = 1240.4±0.1, c = 2623.4±0.2 pm) with 44.9 atoms of Fe, 167.8 atoms of Al and 23.9 atoms of Si and the density was reported to be 3.665 g@cm-3.

[1977Hoi] $-FeAlSi "'-FeAlSi

- -

- -

- -

Found in an Al-0.2 mass% Fe-0.55 mass% Mg-0.6 mass% Si alloy. $-FeAlSi was present in as-cast alloy and it transforms to "'-FeAlSi upon annealing at 580°C for 1 h. The crystal structures of $-FeAlSi and "'-FeAlSi were reported to be monoclinic (a=b=618, c=2080 pm, $=91°) and hexagonal (a=1230, c=2630 pm), respectively.

[1977Sim] "'-Fe5Al20Si2 "-Fe2Al8Si Unknown phase

- - 34.1

- - 65.5

- - <0.5

Found in strip cast Al-0.5 mass% Fe-0.2 mass% Si alloy. The precipitates were characterized by TEM with EDAX analyzer. The crystal structures of "'-Fe5Al20Si2, "-Fe2Al8Si and the unknown phases were cubic (a = 1260 pm), hexagonal and monoclinic (a = 869±6, b = 635±2, c = 632±6 pm, $ = 93.4°±0.5°, isomorphous with Al9Co2), respectively.

[1979Mor] "2-FeAlSi

$-FeAlSi

30.0-33.0 25.0-30.0

64.0-55.0 63.0-55.0

6.0-12.0 12.0-15.0

About 80 extracted particles from the homogenized commercial 6063 aluminium alloy were analyzed by EDAX. The size and Fe/Si ratio in "2-FeAlSi were found to be 3 :m and 2.75 to 5.5, respectively. Similar figures for the $-FeAlSi were 8 :m and 1.6 to 2.25.

[1982Wes] $'-FeAlSi ""-FeAlSi

- -

- -

- -

Found in direct-chilled cast commercial purity Al-Fe-Si alloys. The precipitates were characterized by TEM/STEM and EDAX analyzer. The crystal structures of $'-FeAlSi and ""-FeAlSi were found to be monoclinic (a = 890, b = 490, c = 4160 pm, $ = 92°) and tetragonal (a = 1260, c = 3720 pm), respectively. The Fe/Si ratio in $' was almost unity and that in "" was between 7 and 9.


384


MSIT®

Al–Fe–Si

[1984Don] "v-FeAlSi (Fe3Al12.4-14.6Si1.0-2.1)

31.6-27.0

63.1-63.5

5.3- 9.5

Found in direct-chill cast as well as heat treated (400 to 600°C) three industrial cast alloys. Electrical resistivity and TEM/EDAX were performed to characterize the phases. The crystal structure was reported to be monoclinic (a = 847, b = 635, c = 610 pm, $ = 93.4°).

[1985Don1]"T-FeAlSi (Fe3Al13Si1.0-1.5) "-FeAlSi (Fe3Al13Si1.0-2.0)

30.6-29.929.2-30.7

64.2-62.661.0-64.2

5.2-7.5 9.8- 5.1

Found in both strip cast and direct-chill cast of 10 commercial Al-alloys which were heat treated between 400 to 600°C. The precipitates were analyzed by TEM and the crystal structures of "T-FeAlSi and "-FeAlSi reported to be c-centered monoclinic (a = 2810, b = 3080, c = 2080 pm, $ = 97.74°) and bcc (a = 1250 pm).

[1985Don2]"-FeAlSi "'-FeAlSi $-FeAlSi "v-FeAlSi "T-FeAlSi

- - - - -

- - - - -

-- - - -

Found in a number of strip cast alloys in the range of Al-(0.21 to 2.98) mass% Fe-(0.06 to 1.16) mass% Si, and also after heat treatment at 450°C for 1 week.

[1985Gri] - 31.5 60.7 7.8 Found in as-cast and heat treated Al-(17 to 35) mass% Fe (4 to 14) mass% Si alloy. The precipitates were characterized by X-ray diffraction and EDAX analysis.

[1985Liu], [1986Liu1],

[1986Liu2],

[1987Liu], [1988Liu1],

[1988Liu2]

"-FeAlSi 21-FeAlSi 22-FeAlSi

25.0 25.8 27.8

69.7 70.5 68.8

5.3 3.7 3.4

Dilute Al-Fe-Si alloys with Fe/Si mass ratios of 2 and 4 were studied. Formation of the precipitates was reported to be a function of Fe/Si ratio, alloy purity, solidification rate and alloy heat treatment. The composition and the crystal structures of the phases were analyzed by EDAX and STEM. The crystal structures of "-FeAlSi, 21-FeAlSi and 22-FeAlSi were found to be bcc (a = 1256 pm), c-centered orthorhombic (with Cmmm symmetry and a = 1270, b = 3620, c = 1270 pm) and monoclinic (with Pm symmetry and a = 1250, b = 1230, c = 1930 pm, $ = 109°), respectively. In the commercial alloy with Fe/Si ratio of 2, 21-FeAlSi transformed to 22-FeAlSi upon annealing at 600°C. But in a high purity alloy with Fe/Si ratio of 2, neither 21 nor 22-FeAlSi formed, and "-FeAlSi persisted even after prolonged annealing at 600°C.

[1985Suz] "-FeAlSi $-FeAlSi

32.0 27.0

60.0 59.0

8.0 14.0

The " and $ crystals were extracted from Al-4 mass% Fe-5 mass% Si and Al-4 mass% Fe-10 mass% Si ingots, respectively, which were heat treated at 590 to 640°C for 1 h. The precipitates were characterized by EPMA, X-ray diffraction and Mössbauer spectroscopy.


385


MSIT®

Al–Fe–Si

[1986Dun] "-FeAlSi $-FeAlSi

- -

- -

- -

The " and $ phases were observed after complete crystallization of an Fe14Al74Si12 amorphous alloy obtained by melt-spinning (cooling rate: ~1.5@106 °C/s).

[1987Cha], [1988Cha]

- 27.0-19.0

73.0-78.0

0.0-3.0

Found in Al-6 mass% Fe alloy which was atomized and extruded at 400°C. The crystal structure of the metastable phase was reported to be rhombohedral (with R3c or R3c symmetry, a = 890 pm, " = 111.8°) or hexagonal (a = 1470, c = 780 pm). The above phase was not present after a heat treatment at 450°C for 54 h.

[1987Czi] "-FeAlSi "‘-FeAlSi $-FeAlSi

- --

- - -

- - -

Investigated microstructures of direct-chill cast and heat treated alloys: Al-0.58 mass% Fe-0.28 mass% Si and Al-0.54 mass% Fe-0.95 mass% Si. The as-cast microstructure of first alloy contains "- and "'-AlFeSi precipitates having hexagonal and cubic structure, respectively. The as-cast microstructure of first alloy contains $-AlFeSi precipitates. Isothermal heat treatment at 350, 400, 450, 530 and 600°C resulted in the formation of Fe4Al13 and FeAl6 precipitates.

[1987Gri2] "H-FeAlSi 33.5 58.5 8.0 Alloys close to the composition of Fe2Al8Si were prepared and annealed at 600°C for 1 month. X-ray powder diffraction and EPMA were used to characterize the phase. The hexagonal structure (a = 1240.56±0.7, c = 2623.6±0.2 pm and P6c/mmc symmetry) was confirmed. The details of the powder diffraction data were also presented.

[1987Nag] "C-FeAlSi "H-FeAlSi

- -

- -

- -

A number of ternary alloys in direct-chill cast state and heat treated (450 to 620°C) were investigated by means of X-ray diffraction, EPMA and Mössbauer spectroscopy. "C-FeAlSi was reported to be metastable and decomposes into Fe4Al13 and Si, which in turn react to form "H-FeAlSi.

[1987Skj1] ""-FeAlSi 30.9-32.5

65.4-63.3

3.7- 4.2

Found in direct-chill casting of Al-0.25 mass% Fe-0.13 mass% Si alloy. The precipitates were analyzed by EDAX, TEM and HREM. The crystal structure was reported to be c-centered orthorhombic (a=1300, b=3600, c=1260 pm).

[1987Ste] "-FeAlSi $-FeAlSi (-FeAlSi "2-FeAlSi

28.0-36.0 25.0-28.0 31.0-37.0 40.0-42.0

66.0-51.0 62.0- 56.0 60.0-45.0 48.0-42.0

6.0- 13.0 13.0-16.0 9.0- 18.0 12.0-16.0

Alloys up to 20 to 35 mass% Fe and 4 to 14 mass% Si were investigated. As-cast alloys were reported to contain some non-equilibrium phases. The compositions of the ternary phases were found to depend on the heat treatment. The precipitates were analyzed by means of X-ray diffraction and electron probe microanalysis.


386


MSIT®

Al–Fe–Si

[1987Tur] $-FeAlSi "C-FeAlSi Hexagonal Rhombohedral

- - - -

- - - -

- - - -

$-FeAlSi (having cubic structure) formed in an Al-0.5 mass% Fe-1 mass% Si alloy, whereas "C-FeAlSi, hexagonal and rhombohedral phases formed in an Al-0.5 mass% Fe-0.2 mass% Si alloy. The lattice parameters of latter three phases were a = 1256 pm; a = 1776, c = 1088 pm; a = 2082 pm and " = 95.2°, respectively.

[1988Ben2]"-FeAlSi "'-FeAlSi "''-FeAlSi

- -

- -

- -

Decomposition of rapidly solidified Al-(10 to 14) mass% Fe-2 mass% Si alloys were investigated by TEM. "-FeAlSi forms from an amorphous phase at 380°C and was reported to be metastable and decomposes into "'-FeAlSi and ""-FeAlSi superlattices above 430°C. The crystal structures of "-FeAlSi, "'-FeAlSi and ""-FeAlSi were reported to be cubic (a = 1250 pm), rhombohedral (with R3 symmetry and a = 2080, " = 95.2°) or c-hexagonal (a = 2080, c = 3260 pm) and trigonal (with P3 symmetry and a = 1776, c = 1088 pm), respectively.

[1988Zak] $-FeAl5Si *-FeAl4Si2

25.9-26.6 25.9-27.8

61.3-60.1 48.8-45.8

12.8-13.3 25.3-26.4

$-FeAl5Si has monoclinic structure and *-Fe4Si2 has tetragonal structures and their densities are 3.61 and 3.36 g@cm-3, respectively.

[1993Car] $-Fe3Al10Si2 - - -

$-Fe3Al10Si2 has B-face centered orthorhombic structure with lattice parameters a = 618.4, b = 625, c = 2069 pm. The approximate composition corresponds to the EDS data. However, based on the density data of [1950Phr] and measured unit cell volume, the proposed formula is Fe2Al5Si

[1994Mur][1996Mur]

$-FeAl5Si 19.5-26.8

57.3-67.9

12.5-15.8

Observed in Al-7Si-0.3Mg-0.6Fe, Al-7Si-0.3Mg-0.8Fe, Al-7Si-0.3Mg-0.64Fe-0.27Be and Al-7Si-0.3Mg-1Fe-0.26Be (mass%) alloys.The density of $-phase is 3.29 g@cm-3.

[1996Mul] "-Fe2Al8Si $-FeAl5Si

31.7 25.1

60.0 61.9

8.3 13.0

The " and $ phases were observed in an Al-0.29 mass% Fe-0.58 mass% Si-0.58 mass% Mg alloy. "-Fe2Al8Si forms by L º (Al) + "-Fe2Al8Si, and $-FeAl5Si forms by L+"-Fe2Al8Si º (Al)+$-FeAl5Si. "-Fe2Al8Si is cubic with a = 1250 pm, and $-FeAl5Si is monoclinic with lattice parameters a = b = 612 pm, c = 4150 pm and $ = 91°.

[1999Cho] *-FeAl4Si2 25.9- 61.3-

Observed in Al-8 mass% Fe-20 mass% Si and Al-5 mass% Fe-30 mass% Si alloys, cooled at about 10°C/min. *-FeAl4Si2 has tetragonal structure, and it transforms to equilibrium Fe2Al9Si2 phase at 500°C.


387


MSIT®

Al–Fe–Si

Table 2: Crystallographic Data of Solid Phases

[2000Sri] "-Fe2Al8Si"'-(Fe,Al,Si)$-FeAl5Si(-FeAl3Si

*-FeAl9Si3FeAl4Si2

31.6 32.127.233.0-38.015.025.4

60.652.959.344.0- 54.065.049.1

7.88.713.313.0- 18.020.025.5

Bulk intermetallics prepared from elemental powders by self-propagating high temperature synthesis. However, only "-Fe2Al8Si and FeAl4Si2 were single phase.

[2000Zhe] $-(Fe-Al-Si) - - - Observed in Al-7Si-0.3Mg-0.6Fe (mass%) alloy prepared by [1996Mur]. They found that $-FeAl5Si is actually a multiphase composite. An A-centered orthorhombic phase (space group Cmcm, #63) with a=618, b=620 and c=2080 pm was observed.

[2001Hsu] "C-FeAlSi - -

-

Observed in a model 6xxx alloy containing 0.3 mass% Fe, 0.6 mass% Si and 0.8 mass% Mg. Cubic "C-FeAlSi may form by L+Fe4Al13º (Al)+ "C-FeAlSi and L º (Al)+ "C-FeAlSi. The atomic ratio Al:Fe:Si in "C-FeAlSi may vary from 7:4:1 to 9:5:1.

[2001Kre] J1/J 9: Fe3(Al0.4Si0.6)5J2: Fe2(Al1-xSix)70.2 < x < 0.33 J3: FeAl2.25Si0.75 J4: FeAl3Si2 J5: Fe2Al7.4Si J6: FeAl4.5Si J7: FeAl1.5Si1.5 J8: FeAl0.67Si1.33 J10: Fe5Al12Si3

- -

-------

--

-------

--

-------

All ternary phases exist at 550°C. Previously reported J1 and J9 [1992Gho] are established as one phase with large homogeneity range.

[2001Sha] "-FeAlSi$-FeAlSi

--

--

--

Observed in a model 6xxx alloy containing 0.3 mass% Fe, 0.6 mass% Si and 0.8 mass% Mg. "-FeAlSi may be simple cubic with a = 1252 pm, or bcc with a = 1256 pm. $-FeAlSi is monoclinic. They may form by the following reactions: L+Fe4Al13º(Al)+"-FeAlSi, Lº(Al)+ "-FeAlSi, and L+"-FeAlSiº(Al)+$-FeAlSi. $-FeAlSi is metastable.

Phase/Temperature Range[°C]

Pearson Symbol/Space Group/Prototype

Lattice Parameters[pm]

References/Comments

(Al) # 660.452

cF4Fm3mCu

a = 404.88 pure Al at 24°C [V-C]

("Fe) # 1538

cI2Im3m W

a = 286.65 pure Fe at 20°C [V-C]


388


MSIT®

Al–Fe–Si

(Si) # 1414

cF8Fm3mC-diamond

a = 543.088 a = 542.86

at 20°C and 99.999 at.% purity [V-C] at 20°C and 99.97 at.% purity [V-C]

"1, Fe3Al # 552.5

cF16Fm3mBiF3

a = 578.86 to 579.3 [2003Pis], solid solubility ranges from 22.5 to 36.5 at.% Al

"2, FeAl # 1310

cP2Pm3m CsCl

a = 289.76 to 290.78 [2003Pis], at room temperature solid solubility rangesfrom 22.0 to 54.5 at.% Al

g, Fe2Al3 1102-1232

cI16? a = 598.0 [2003Pis], solid solubility ranges from 54.5 to 62.5 at.% Al

FeAl2 # 1156

aP18P1 FeAl2

a = 487.8 b = 646.1 c = 880.0" = 91.75°$ = 73.27°( = 96.89°

[2003Pis], at 66.9 at.% Alsolid solubility ranges from 65.5 to 67.0 at.% Al

0, Fe2Al5 # 1169

oC24Cmcm

a = 765.59 b = 641.54 c = 421.84

[2003Pis], at 71.5 at.% Al solid solubility ranges from 71.0 to 72.5 at.% Al.

Fe4Al13# 1160

mC102C2/m Fe4Al13

a = 1552.7 to 1548.7 b = 803.5 to 808.4 c = 1244.9 to 1248.8$ = 107.7 to 107.99°a = 1549.2b = 807.8c = 1247.1$ = 107.69°

[2003Pis], 74.16 to 76.7 at. % Al solid solubility ranges from 74.5 to 75.5 at.% Al

[2003Pis], at 76.0 at.% Al.Also denoted FeAl3 or Fe2Al7

"1, Fe3Si # 1235

cF16Fm3m BiF3

a = 565.54 [V-C]; 11.0 to 30.5 at.% Si [Mas]

"2 # 1280

cP2Pm3mCsCl

- 10.0 to 23.5 at.% Si [Mas]

Fe2Si 1212-1040

hP6P63/mmc Fe2Si

a = 405.2 c = 508.55

[V-C]; 33.0 to 34.5 at.% Si [Mas]

Fe5Si3 1060-825

hP16P63/mmc Mn5Si3

a = 675.52 c = 471.74

[V-C]

FeSi # 1410

cP8P213 FeSi

a = 448.91 [V-C]; 49.0 to 51.0 at.% Si [Mas]

FeSi2(h) 1220-937

tP3P4/mmmFeSi2

a = 269.5 c = 509.0

[V-C]; 69.5 to 73.0 at.% Si [Mas]




References/Comments

389


MSIT®

Al–Fe–Si

FeSi2(r) # 982

oC48 FeSi2

a = 986.3 b = 779.1 c = 783.3

[V-C]

* J1/J9, Fe3Al2Si3

-

aP16P1Fe3Al2Si3

-

a = 465.1b = 632.6c = 749.9" = 101.37°$ = 105.92°( = 101.23°a = 462.3b = 637.4c = 759.9" = 102.81°$ = 105.6°( = 100.85°a = 469.1b = 632.5c = 751.1" = 100.6°$ = 105.5°( = 101.78°a = 468.7b = 633.1c = 751.9" = 100.43°$ = 105.44°( = 101.63°

[1940Tak], likely to correspond to the E-phase of [1974Mur] and [1981Zar]. D-phase of [1981Zar] and J9 of [1992Gho].[1996Yan], Fe3Al2Si3 annealed at 600°C

[2001Kre], at Fe38.2Al29Si32.8

[2001Kre], at Fe38Al35Si27


* J2, (-AlFeSi, Fe2Al5Si2

- c** mC*

m**

- a = 1603.23 a = 890.0 b = 1025.0 c = 1780.0 $ = 132.0° a = 889.3b = 1018.8c = 1766.9$ = 132.18°

a = 420.0 b = 760.0 c = 1533.0 $ = 89.0°

at Fe6Al12Si6 [1940Tak] [1952Arm, 1955Arm], in an Al-35.3 mass% Fe-12.8 mass% Si alloy [1967Mun], Fe19.4-23Al59-61.4 Si27.6-15.6 and is likely to correspond to the K-phase of [1974Mur] and [1981Zar][2001Kre], at Fe22Al60Si18

[1974Mur, 1981Zar]. K-phase at Fe22Al63-52Si15-26. Annealed at 600°C.




References/Comments

390


MSIT®

Al–Fe–Si

* J3, Fe5Al9Si5,FeAl2Si

- oC128CmmaFeAl2Si

- a = 768.0 b = 1530.0 c = 1600.0

a = 799.5b = 1516.2c = 1522.0

a = 726.2b = 1551.2c = 1550.6

a = 795.8b = 1517.8c = 1523.7

[1940Tak], likely to correspond to the G-phase of [1974Mur] and [1981Zar] [1974Mur, 1981Zar], G-phase at FeAl2Si. Annealed at 600°C.

[1989Ger2] at 600°C,Fe25Al50Si25



* J4, *-AlFeSi,FeAl3Si2 tI24

I4/mcm PdGa5

a = 607.0 c = 950.0

a = 615.0 c = 947.0

a = 612.23 c = 947.91

a = 612.23 c = 948.91

a = 612.0 c = 953.0

a = 630.0 c = 941.0

a = 606.1 c = 952.5

a = 608.74 c = 951.36

[1940Tak], at FeAl3Si [1969Pan], annealed at 800°C for 14 h and water quenched.

[1936Jae], at FeAl4Si2. In an Al-27.04Fe-25.01Si (mass%) alloy

[1950Phr], an Al-15 mass% Fe-20 mass% Si alloy

[1954Spi]

[1974Mur, 1981Zar], A-phase at FeAl2.76Si2.24. Annealed at 600°C.

[1974Mur, 1981Zar], A-phase at FeAl3.35Si1.65. Annealed at 600°C.

[1995Gue1]

[2001Kre], at Fe16.9Al49.5Si33.3. Singlephase at 700°C.




References/Comments

391


MSIT®

Al–Fe–Si

* J5, "-AlFeSi,Fe2AL7.4SiFe46(Al0.875Si0.125)200-xx.7

- hP245P63/mmc Fe2Al7.4Si

- a = 1240.4 c = 2623.4 a = 1240.56 c = 2623.6

a = 1239.4 c = 2621.0

a = 1239.2 c = 2619.3

a = 1241.0c = 2626.4

a = 1230.0 c = 2630.0

a = 1230.0 c = 2630.0

a = 1230.0 c = 2620.0

a = 1230.0 c = 2630.0

a = 1240.06 c = 2622.41

a = 1238.9 c = 2625.5

a = 1239.86 c = 2621.9

[1940Tak], at Fe6Al15Si5 [1977Cor], at Fe1.9Al7.1Si. Likely to correspond to the M-phase of [1974Mur] and [1981Zar]. [1987Gri2], at Fe2.1Al7.6Si. Annealed at 600°C for a month.

[1987Gri2], 9.5 ± 5 mass% Si in J5.Annealed at 600°C for a month.

[1987Gri2], 9.0 ± 5 mass% Si in J5. Annealed at 600°C for a month.

[1987Gri2], 7.0 ± 4 mass% Si in J5. Annealed at 600°C for a month.

[1975Bar], at Fe1.95Al7.93Si

[1953Rob]

[1967Mun]

[1977Hoi]

[1997Vyb], at Fe19.2Al71.2Si9.6






References/Comments

392


MSIT®

Al–Fe–Si

* J6, $-AlFeSiFe2Al9Si2

- C2/cmC52 Fe2Al9Si2

oC?Cmcm

t** -

- a = 612.23 b = 612.23 c = 4148.36 $ = 91.0° a = 612.23 b = 612.23 c = 4148.36 $ = 91.0° a = 612.2 b = 612.2 c = 4148.4 $ = 91.0° a = 612.0 b = 612.0 c = 4150.0 $ = 91.0° a = 2081.3b = 617.5c = 616.1$ = 90.42°a = 612b = 612c = 4150$ = 91°a = 579.2b = 1227.3c = 431.3$ = 98.9°a = 615.59 to 620.89b = 616.87 to 619.78c = 2076.7 to 2081.2$ = 90.1° to 90.6°a = 2079.7b = 616.9c = 616.87$ = 90.01°a = 2082.7b = 616.6c = 616.71$ = 90.01°a = 618.4b = 625.0c = 2069.0a = 618.0b = 620.0c = 2080.0a = 618.0 c = 4250.0

[1940Tak], at FeAl4Si [1950Phr], Fe2Al9Si2. Composition may vary from 27.2 to 27.4 mass% Fe and 13.5 to 13.6 mass% Si. Likely to correspond to the L-phase of [1974Mur] and [1981Zar].[1954Spi] [1955Obi] [1975Bar], at Fe2Al10.26Si2.06 [1994Rom]

[1996Mul], at Fe14Al71.6Si14.4

[1994Mur, 1996Mur]

[1997Vyb]

[2001Kre], at Fe15Al68.5Si16.5


[1993Car]

[2000Zhe]

[1955Bla], at Fe2Al8.98Si2




References/Comments

393


MSIT®

Al–Fe–Si

Table 3: Classification of Metastable Phases Based on the Crystal System

* J7, Fe22Al40Si38Fe(Al0.5Si0.5)3

P21/cmP64Fe2Al3Si3

-

a = 717.9b = 835.4c = 1445.5$ = 93.8a = 718.9b = 831.7c = 1454.2$ = 93.48

[1974Mur, 1981Zar], B-phase. Annelaed at 600°C.[1995Gue2] at 800°C

[2001Kre] at Fe25.3Al45Si29.7

* J8, Fe3Al2Si4,Fe(Al0.33Si0.67)2

oC36CmcmFe3Al2Si4

-

a = 366.8b = 1238.5c = 1014.7a = 366.7b = 1236.2c = 1014.0

[1974Mur, 1981Zar], C-phase.Fe32Al38Si30 Annealed at 600°C.[1996Yan], at Fe3Al2Si4 annealed at 500°C

[2001Kre]

* J10, Fe5Al12Si3Fe(Al0.8Si0.2)3

hP26 or hP28P63/mmc Mn3Al10 or Co2Al5

a = 752.6 c = 763.2

a = 750.9c = 759.4a = 1551.8c = 729.7

[1974Mur, 1981Zar], F-phase in the as-cast sample. The crystal structure of F-phase after annealing at 600°C is different from that in the as-cast samples.[1989Ger1], at Fe1.7Al4Si


Phase Designation

Crystal System

Composition (mass%) Lattice Parameters [pm]

ReferencesFe Al Si

:1 Cubic 25.4 31.9 27.3 - 30.2- 32.831.9 - 31.1 - 29.2-30.725.0 - -

49.1 62.5 65.7 - 58.1- 60.0 61.7 - 60.8 - 61.0-64.269.7 - -

25.5 5.6 7.0 - 11.7- 7.2 6.4 - 8.1 - 9.8- 5.1 5.3 - -

- a = 1254.83 a = 1254.83 a = 1254.53 a = 1254.8 a = 1256.0 a = 1250 to 1270a = 1250±10 a = 1260.0 a = 1250a = 1256.0 a = 1256.0 a = 1250a = 1250

[1937Ser] [1950Phr] [1952Arm], [1955Arm] [1954Spi] [1955Obi] [1967Coo] [1967Mun] [1967Sun] [1977Sim] [1985Don1] [1986Liu1, 1986Liu2, 1987Liu][1987Tur] [1988Ben2][1996Mul]

:2 Tetra- gonal

- -

- -

- -

a = 495.0 c = 707.0 a = 1260.0 c = 3720.0

[1951Now] [1982Wes]




References/Comments

394


MSIT®

Al–Fe–Si

:3 Ortho- rhombic

-

29.2

25.8

30.9-32.5

-

59.5

70.5

65.4-63.3

-

11.3

3.7

3.7- 4.2

a = 609.0 b = 996.0 c = 374.0

a = 4360.0 b = 4960.0 c = 7080.0

a = 1270.0 b = 3620.0 c = 1270.0

a = 1300.0 b = 3600.0 c = 1260.0

[1936Jae]

[1952Arm], [1955Arm], [1967Mun]

[1986Liu1], [1986Liu2], [1987Liu]

[1987Skj1]

:4 Rhombo- hedral

27.0-19.0

-

-

73.0-78.0

-

-

0.0- 3.0

-

-

a = 890.0 "= 111.8°

a = 2082.0 " = 95.2°

a = 2080.0 " = 95.2°

[1987Cha], [1988Cha]

[1987Tur]

[1988Ben2]

:5 Hexagonal -

29.2

27.0-19.0

-

-

-

59.5

73.0-78.0

-

-

-

11.3

0.0-3.0

-

-

a = 836.0 c = 1458.0

a = 496.0 c = 702.1

a = 1470.0 c = 780.0

a = 1776.0 c = 1088.0

a = 1776.0 c = 1088.0

[1936Jae]

[1952Arm], [1955Arm], [1967Mun]

[1987Cha], [1988Cha]

[1987Tur]

[1988Ben2]

Phase Designation

Crystal System


ReferencesFe Al Si

395


MSIT®

Al–Fe–Si

Table 4: Invariant Equilibria

:6 Mono- clinic

32.1-32.7- 34.1 - 31.6-27.0

30.6-29.9

27.8

59.5-57.0- 65.5 - 63.1-63.5

64.2-62.6

68.8

8.4-10.3- < 0.5 - 5.3- 9.5

5.2- 7.5

3.4

- a = 618.0 b = 618.0 c = 2080.0 $ = 91.0° a = 869.0 ± 6 b = 635.0 ± 2 c = 632.0 ± 6 $ = 93.4 ± 0.5°a = 890.0 b = 490.0 c = 4160.0 $ = 90.0° a = 847.0 b = 635.0 c = 610.0 $ = 93.4° a = 2810.0 b = 3080.0 c = 2080.0 $ = 97.74° a = 1250.0 b = 1230.0 c = 1930.0 $ = 109.0°

[1951Pra2] [1977Hoi] [1977Sim] [1982Wes] [1984Don] [1985Don1] [1986Liu1], [1986Liu2], [1987Liu]

:7 Triclinic - - - a = 688.0 b = 593.0 c = 432.0 " = 104.75° $ = 130.67° ( = 68.4°

[1936Jae]

Reaction T [°C] Type Phase Composition (mass%)Fe Al Si

L + Fe2Si º "1 + FeSi . 1180 U1 - - - -L + g º "2 + Fe2Al5 1120 U2 L

g, Fe2Al3 "2Fe2Al5

51.0 56.5 58.0 45.0

46.0 43.0 28.0 52.0

3.0 0.5 14.0 3.0

L + "1 + FeSi º J1 1050 P1 L "1FeSi J1

50.0 63.0 66.3 55.0

31.0 26.0 0.4 26.6

19.0 11.0 33.3 18.4

L + "2 º Fe2Al5 + J1 1030 U3 L "2Fe2Al5 J1

48.5 65.0 45.0 55.0

37.5 25.0 52.5 26.6

14.0 10.0 2.5 18.4

Phase Designation

Crystal System


ReferencesFe Al Si

396


MSIT®

Al–Fe–Si

L + Fe2Al5 º Fe4Al13 + J1 1020 U4 L Fe2Al5 Fe4Al13 J1

48.0 45.0 39.2 55.0

38.0 52.5 60.0 26.6

14.0 2.5 0.8 18.4

L + FeSi º FeSi2(h) + J1 1000 U5 L FeSi FeSi2(h) J1

42.0 66.3 44.8 55.0

26.0 0.4 0.5 26.6

32.0 33.3 54.7 18.4

L + Fe4Al13 + J1 º J2 940 P2 L Fe4Al13 J1 J2

40.0 39.2 55.0 41.9

41.0 60.0 26.6 40.5

19.0 0.8 18.4 17.6

L + J1 + J2 º J7 935 P3 L J1 J2 J7

39.0 55.0 41.9 42.2

39.0 26.6 40.5 36.7

22.0 18.4 17.6 21.1

L + J1 º FeSi2(?) + J7 885 U6 L J1 FeSi2(?) J7

28.0 55.0 49.7 42.2

36.0 26.6 0.5 36.7

36.0 18.4 49.8 21.1

L + FeSi2(?) º J7 + (Si) 880 U7 L FeSi2(?) J7 (Si)

26.0 49.7 42.2 0.01

38.0 0.5 36.7 0.013

36.0 49.8 21.1 99.977

L + J7 + (Si) º J4 865 P4 L J7 (Si) J4

23.0 42.2 0.01 28.9

45.0 36.7 0.013 41.9

32.0 21.1 99.977 29.2

L + Fe4Al13 + J2 º J5 855 P5 L Fe4Al13 J2 J5

25.0 39.2 41.9 38.1

58.0 60.0 40.5 46.0

17.0 0.8 17.6 15.9

L + J7 º J2 + J4 835 U8 L J7 J2 J4

22.0 42.2 41.9 28.9

56.0 36.7 40.5 41.9

22.0 21.1 17.6 29.2

L + J2 º J4 + J5 790 U9 L J2 J4 J5

18.0 41.9 28.9 38.1

61.0 40.5 41.9 46.0

21.0 17.6 29.2 15.9

L + J4 + J5 ºJ6 700 P6 L J4 J5 J6

7.2 28.9 38.1 29.1

78.8 41.9 46.0 56.3

14.0 29.2 15.9 14.6

L + Fe4Al13 º (Al) + J5 632 U10 L Fe4Al13 (Al) J5

2.0 39.2 0.05 38.1

93.8 60.0 99.31 46.0

4.2 0.8 0.64 15.9


397


MSIT®

Al–Fe–Si

Table 5: Coordinates of the (/("+() and ("+()/" Phase Boundaries in the Al-Fe-Si System

L + J5 º (Al) + J6 613 U11 L J5 (Al) J6

1.8 38.1 0.04 29.1

92.0 46.0 98.96 56.3

6.2 15.9 1.0 14.6

L + J4 º J6 + (Si) 600 U12 L J4 J6 (Si)

1.5 28.9 29.1 0.01

84.2 41.9 56.3 0.012

14.3 29.2 14.6 99.978

L º J6 + (Al) + (Si) 573 E1 L J6 (Al) (Si)

0.5 29.1 0.01 0.01

87.8 56.3 98.34 0.01

11.7 14.6 1.65 99.98

Composition mass% Temperature [°C] of the Al Si (/("+() boundary ("+()/" boundary0.16 0.19 0.31 0.44 0.44 0.48 0.64 0.71 0.74

0.25 0.58 0.93 0.19 0.53 0.13 0.23 0.65 0.24

905 952 1014 935 976 948 1030 1048 1000

1385 1351 1300 1350 1326 1347 1275 1270 1303


20

40

60

80

20 40 60 80

20

40

60

80

Fe Al

Si Data / Grid: at.%

Axes: at.%

τ1 [1940Tak]

τ2

τ3

τ4

τ5 [1940Tak]

τ6

τ7 [1974Mur, 1981Zar]

τ8 [1974Mur, 1981Zar]τ9 [1974Mur, 1981Zar]

τ5

[1974Mur, 1981Zar]

[1974Mur, 1981Zar]

[1974Mur, 1981Zar]

[1940Tak]

[1940Tak]

[1940Tak]

[1936Jae]

τ10 [1974Mur, 1981Za

[1985Gri2] [1975Bar][1977Cor]

[1967Mur][1955Obi][1950Phr]

[1950Phr]

[1955Bla]

[1975Baz]

τ5 [2001Kra]

τ10 [2001Kre]

τ3 [2001Kre]

τ1/τ9 [2001Kre]

τ8 [2001Kre]τ8 [1996Yan]

[2001Kre][1988Zak]

[2001Kre, 1988Za[1996Mul]

τ7 [2001Kre]

[1974Mur, 1981Zar]

Fig. 1: Al-Fe-Si.Distribution of the equilibrium ternary phases, as reported by different authors

398


MSIT®

Al–Fe–Si

10

20

30

40

60 70 80 90

10

20

30

40

Fe 50.00Al 50.00Si 0.00

Al

Fe 0.00Al 50.00Si 50.00 Data / Grid: at.%

Axes: at.%

[1986Lin1,1986Lin2, 1987Lin][1986Lin1, 1986Lin2, 1987Lin]

µ6µ3[1987Skj1][1977Sim]

µ1

[1952Arm][1985Don1]

[1985Don1][1984Don][1950Phr]

[1967Coo][1955Obi]

[1955Obi]

µ4 or µ5[1987Cha, 1988Cha]

[1951Bra2]

µ6

[1967Sun]µ6

[1984Don]

[1952Arm, 1967Mun], µ3 or µ4

µ1

[1968Don]

µ1, [1937Ser]

10 200

250

500

750

1000

1250

1500

Fe 75.00Al 25.00Si 0.00

Fe 75.00Al 0.00Si 25.00Si, at.%

Tem

pera

ture

, °C

(αFe)

1223°C

750°C

550°C

α2(B2)

α1(DO3)

640°C

460°C

(αFe)+α1+α2

(αFe)+α1

(αFe)+α2

Fig. 2: Al-Fe-Si.Distribution of the metastable ternary phases, as reported by different authors

Fig. 3: Al-Fe-Si.The Fe3Al-Fe3Si sections showing the boundaries of "1 (D03), "2 (B2) and ("Fe) (disordered bcc) phases

399


MSIT®

Al–Fe–Si

Fig

. 4a:

Al-

Fe-

Si. R

eact

ion

schem

e, p

art

1

Al-

Fe

Fe-

Si

A-B

-CA

l-F

e-S

iA

l-S

i

l + α

2ε

12

32

p1

L+

Fe 2

Si

α 1+

FeS

ica

.11

50

U1

l F

eSi+

FeS

i 2(h

)

12

12

e 1

l F

eSi 2

(h)+

(Si)

12

07

e 2

l F

eSi+

Fe 2

Si

12

03

e 3

lα 1

+ F

e 2S

i

12

00

e 4

lη

+ε

11

65

e 5

L +

α2

η+

τ 11

030

U3

L +

η F

e 4A

l 13

+τ 1

10

20

U4

Fe 2

Si+

FeS

i F

e 5S

i 3

10

60

p3

Fe 2

Si

Fe 5

Si 3

+F

e 3S

i

10

40

e 8

FeS

i+F

eSi 2

(h)

FeS

i 2(r

)

98

2p4

FeS

i 2(h

)F

eSi 2

(r)+

(Si)

93

7e 9

ε +

η F

eAl 2

11

56

p2

lη

+ F

e 4A

l 13

11

60

e 6

εα 2

+ F

eAl 2

11

02

e 7L

+ ε

α 2+

η1

120

U2

L +

α1

+ F

eSi

τ 11

050

P1

L +

FeS

i F

eSi 2

(h)

+ τ1

10

00

U5

L+

τ 1 +

τ2

τ 79

35

P3

L +

Fe 4

Al 13

+τ 1

τ 29

40

P2

L +

τ1

FeS

i 2(r

) +

τ7

88

5U6

L+

α 1+

FeS

iF

eSi+

α 1+

Fe 2

Si

L+

α 2+

ηε+

α 2+

η

α 1+

FeS

i+τ 1

L+

FeS

i+τ 1

FeS

i+F

eSi 2

(h)+

τ 1

L+

FeS

i 2(r

)+τ 7

τ 1+

FeS

i 2(r

)+τ 7

L+

τ 2+

τ 7

τ 7+τ

1+

τ 2

Fe 4

Al 13+L

+τ 2

Fe 4

Al 1

3+L

+τ 1

Fe 4

Al 13+η

+τ 1

α 2+η

+τ 1

η+L

+τ 1L

+α 1

+τ 1

L+

τ 1+

τ 2

L+

τ 1+

τ 7

L+

FeS

i 2(h

)+τ 1

Fe 4

Al 13+

τ 1+

τ 2

400


MSIT®

Al–Fe–Si

Fig

. 4b:

Al-

Fe-

Si. R

eact

ion s

chem

e, p

art

2

Al-

Fe

Fe-

Si

A-B

-CA

l-F

e-S

iA

l-S

i

L +

FeS

i 2(r

)τ 7

+ (

Si)

88

0U7

L +

τ7

+ (

Si)

τ 4

86

5P4

L +

τ7

τ 2+

τ 48

35

U8

L +

Fe 4

Al 13

+τ 2

τ 58

55

P5

L +

τ2

τ 4+

τ 57

90

U9

L +

τ4

+τ 5

τ 67

00

P6

l F

e 4A

l 13

+ (

Al)

65

5e 11

L +

Fe 4

Al 13

(A

l) +

τ5

63

2U10

L +

τ5

(A

l) +

τ6

61

3U11

L +

τ4

τ 6+

(S

i)6

00

U12

Lτ 6

+ (

Al)

+ (

Si)

57

3E1

l (

Al)

+ (

Si)

57

7e 12

Fe 5

Si 3

α 2+

FeS

i

82

5e 10

L+

(Al)

+τ 6

τ 5+

(Al)

+τ 6

τ 6+

(Al)

+(S

i)

τ 4+

τ 6+

(Si)

L+

τ 6+

(Si)

FeS

i 2(r

)+τ 7

+(S

i)L

+τ 7

+(S

i)

τ 7+

(Si)

+τ 4 τ 7

+τ 2

+τ 4

τ 2+

τ 4+

τ 5L

+τ 2

+τ 5

L+

τ 7+

τ 4

L+

(Si)

+τ 4

Fe 4

Al 13+

(Al)

+τ 5

L+

(Al)

+τ 5

L+

τ 4+

τ 6L

+τ 5

+τ 6

τ 4+

τ 5+

τ 6

Fe 4

Al 13+

τ 2+

τ 5L

+τ 2

+τ 5

L+

FeS

i 2(h

)+(S

i)L

+F

eSi 2

(r)+

τ 7

L+

τ 2+

τ 7

L+

τ 2+

Fe 4

Al 13

L+

Fe 4

Al 13+

τ 5L+

τ 2+

τ 4

401


MSIT®

Al–Fe–Si

Si, mass%

Fe,mass%

2

0

Al10

2

3

4

5

6

0

1

4 6 8 12 14 16

(Al)

650°C

660°C

670°C680°C

690°C

700°C

710°C720°C730°C740°C750°C760°C770°C780°C

640°C

620°C

620°C

610°C

610°C

600°C

590°C

580°C

630°C

(Si)

U11

P6

U12

E1

U10

Fe Al 13

4 �5

�2

�6

�4

20

40

60

80

20 40 60 80

20

40

60

80

Fe Al


Axes: at.%

1400

1350

1300

12501207°C,e2

FeSi2(h)

1212°C, e1

(Si)

1050

1000950

900P4

U7

τ1

U5

P1

U3

P2

U8τ7

U9P5τ2

U6

900

U4

τ5

τ6

(Al)U10

U11

P6 U12e12

700

750800

850

U2

Fe2 Al

5

Fe4 Al

13

τ4

655°C,e11

13501300 1250 1150

FeSi

Fe2Si U1

α2

1300

1350

1200

1100

1200°C, e4

1203°C, e3

1400

1500

1232°C, p1 1165°C, e5 1160°C, e6

(αFe)

α2

α1

ε

E1

P3

1200

Fig. 6: Al-Fe-Si.Liquidus surface

Fig. 5: Al-Fe-Si.Calculated liquidus surface of Al-corner [1999Liu]

402


MSIT®

Al–Fe–Si

10

90

10

Fe 20.00Al 80.00Si 0.00

Al


Axes: at.%

L+τ4

L+τ4+τ6

L+τ6

L+τ5+τ6

L+τ5

L

L+Fe4Al13+τ5

L+Fe4Al13

L+(Al)

L+(Al)+Fe4Al13(Al)

(Al)+Fe4Al13

20

40

60

80

20 40 60 80

20

40

60

80

Fe Al


Axes: at.%

FeSi2(h)+L+(Si)

L+(Si)

L

L+FeSi2(h)FeSi

2 (h)+L+τ1

FeSi2(h)

FeSi2 (h)+τ

1 +FeSi

L+τ1

τ1

τ1 +η+α

2

L+Fe4Al13

τ1+L+Fe4Al13

Fe4Al13

Fe4Al13+τ1+Fe2Al5

FeAl2 η

α2+η

α1+τ1

α2

α1+FeSi

α1+Fe5Si3+FeSiFeSi+τ

1 +α1

FeSi

Fe5Si3

α1+Fe5Si3

(γFe) (γFe)+(αFe)

(αFe)

α1

Fig. 7: Al-Fe-Si.Isothermal section at 1000°C

Fig. 8: Al-Fe-Si.Isothermal section of the Al-corner at 640°C

403


MSIT®

Al–Fe–Si

20

40

60

80

20 40 60 80

20

40

60

80

Fe Al


Axes: at.%

Fe4Al13ηFeAl2(αFe)+α2

α2

α1+α2

FeSi

FeSi2

(Si)+FeSi2

(Si)

(Al)+(Si)

(Al)

(Al)+(Si)+τ

4

τ4 +τ

7 +(Si)

(Si)+FeSi2 +τ7

τ7+τ8+FeSi2τ8+FeSi2+FeSi

τ1/τ9+FeSi+α2

(αFe)+α1

(αFe)

α1

α2

α2+τ1/τ9+η

FeAl2+α2 (Al)+τ5+Fe4Al13

(Al)+τ6+τ4τ6

τ5

τ10

τ2

τ7

τ3

τ1/τ9

α1+FeSiτ4

τ8

τ1 /τ

9 +τ8 +τ

10

τ1 /τ

9 +FeSi+τ8

10

20

30

70 80 90

10

20

30

Fe 40.00Al 60.00Si 0.00

Al


Axes: at.%

τ2

τ5

Fe4Al13

(Al)+Fe4Al13+τ5

(Al)

(Al)+τ6+(Si)(Al)+τ5+τ6

τ6

Fig. 10: Al-Fe-Si.Isothermal section at 600°C

Fig. 9: Al-Fe-Si.Isothermal section of the Al-corner at 570°/600°C, see text

404


MSIT®

Al–Fe–Si

Fe 1.00Al 99.00Si 0.00

Al


Axes: at.%

(Al)+τ6+(Si)

(Al)+(Si)

(Al)

(Al)+τ5

(Al)+τ5+τ6

(Al)+τ6

(Al)+Fe4Al13

(Al)+τ5+Fe4Al13

20

40

60

80

20 40 60 80

20

40

60

80

Fe Al


Axes: at.%

(Al)+(Si)+τ

6

τ6α2

τ8

FeSi2

FeSi

ηFeAl2 Fe4Al13

τ4τ1/τ9 τ7

τ2

τ3τ10 τ5

FeSi+FeSi2+τ

8 (Si)+τ8+τ7

(Si)+τ7 +τ

4

(Si)

(Al)

FeSi

2+τ

8+(

Si)

Fig. 12: Al-Fe-Si.Isothermal section of the Al-corner at 500°C

Fig. 11: Al-Fe-Si.Partial isothermal section at 550°C

405


MSIT®

Al–Fe–Si

70

80

90

10 20 30

10

20

30

Fe Fe 60.00Al 40.00Si 0.00


Axes: at.%

(αFe)

(αFe)+α1

α2 α1+α2

α1+α2

α1 α2

70

80

90

10 20 30

10

20

30

Fe Fe 60.00Al 40.00Si 0.00


Axes: at.%

(αFe)α2

α1

Fig. 14: Al-Fe-Si.Isothermal section of the Fe-corner at 650°C


406


MSIT®

Al–Fe–Si

70

80

90

10 20 30

10

20

30

Fe Fe 60.00Al 40.00Si 0.00


Axes: at.%

α2

α1+α2

α1

(αFe)+α1

α1+α2

(αFe)

α2


70

80

90

10 20 30

10

20

30

Fe Fe 60.00Al 40.00Si 0.00


Axes: at.%

(αFe)

α1+α2

(αFe)+α1

α1 α2

α2


407


MSIT®

Al–Fe–Si

10400

500

600

700

800

Fe 1.97Al 98.03Si 0.00

Fe 1.98Al 83.22Si 14.80Si, at.%

Tem

pera

ture

, °C

(Al)+τ6+(Si)(Al)+Fe4Al13+τ5

(Al)+Fe4Al13

(Al) +τ5

(Al)+τ5+τ6

(Al)+τ6

(Al)+L+τ6 L+τ6+(Si)

L+τ4+τ6

L+τ4

L+τ6

L+τ5+τ6

L+τ5

L+Fe4Al13+τ5(Al)+L+Fe4Al13

(Al)+τ5+L

L+Fe4Al13

L

632°C

613°C

573°C

600°C

Fig. 18: Al-Fe-Si.Polythermal section at a constant Fe content of 4.0 mass%

10500

600

700

Fe 0.30Al 99.70Si 0.00

Fe 0.30Al 80.30Si 19.40Si, at.%

Tem

pera

ture

, °C

Fe4Al13+(Al)

(Al)+Fe4Al13+τ5

(Al)+τ5

(Al)+τ5+τ6

τ6+(Al)

L+τ6+(Al)

(Al)+(Si)+τ6

L+(Si)+τ6

L+(Si)+τ4

L+(Si)

L+τ5+(Al)

L+(Al)

11.33 at.%573

613

L+(Al)+Fe4Al13655°C, e11

632

L

Fig. 17: Al-Fe-Si.Polythermal section at a constant Fe content of 0.7 mass%

408


MSIT®

Al–Fe–Si

400

500

600

700

Fe 2.00Al 90.10Si 7.90

Fe 0.00Al 92.30Si 7.70Al, at.%

Tem

pera

ture

, °C

LL+τ5

L+τ5+τ6

L+τ5+Fe4Al13

L+Fe4Al13

L+τ6

(Al)+L+τ6 573°CL+(Al)

(Al)+τ6+(Si)

(Al)+(Si)

L+(Al)+(Si)

91 92

Si, mass%

Fe,mass%

10-3

�

0.2

0

Al

0.4 0.6 0.80 1.0 1.2 1.4 1.6 1.8

10

15

20

25

30

35

40

45

50

5

�6

�5

(Si)

Fe Al4 13

640°C

630°C

620°C

610°C

590°C

580°C570°C

560°C550°C530°C510°C490°C470

450

600°C

Fig. 19: Al-Fe-Si.Polythermal section at a constant Sicontent of 8.0 mass%

Fig. 20: Al-Fe-Si.(Al)-solidus (dash lines) and -solvus (solid lines) surfaces, calculated using the dataset of [1999Liu]

409


MSIT®

Al–Fe–Si

Fe, mass%

Si,mass%

1

0

Al2 3 4 5 60

2

4

6

12

10

8

e , 577°C12

e , 655°C11

secondary (Al)

650°C

640°C

630°C

sec. FeAl3

650°C

640°C

sec. �5

U10

sec.

� 6

U11

E1

sec.

(Si)

sec. (Si)

sec. �6

tern. (Si)

640°C

650°C

660°C

660°C

tern. �6

sec. �6

670°C

620°

C

sec.

� 5

620°C

600°C

590°C

600°C

580°C

590°C

sec. (Al)

sec. (Al)

tern. (Al)

630°C

secondary �5

ternary (Al)

615°C

615°C

620°C 630°C

Fig. 21: Al-Fe-Si.Surface of secondary crystalization of Al-corner

Documents

Aluminium – Iron – Siliconextras.springer.com/2005/978-3-540-23118-9/00400011a2/... · Aluminium – Iron – Silicon Gautam Ghosh Literature Data ... where xAl is the atomic