Light Metal Systems. Part 3: Selected Systems from Al-Fe-V to Al-Ni-Zr

470 Pages·2005·5.68 MB·English

by  G. Effenberg

Intro d u c t i o n XI
Introduction
Data Covered
The seriesfocuses on light metal ternary systems and includes phase equilibria of importance for alloy
development, processing or application, reporting on selected ternary systems of importance to industrial
light alloy development and systems which gained otherwise scientific interest in the recent years.
General
The series provides consistent phase diagram descriptions for individual ternary systems. The
representation of the equilibria of ternary systems as a function of temperature results in spacial diagrams
whose sections and projections are generally published in the literature. Phase equilibria are described in
terms of liquidus, solidus and solvus projections, isothermal and pseudobinary sections; data on invariant
equilibria are generally given in the form of tables.
The world literature is thoroughly and systematically searched back to the year 1900. Then, the
published data are critically evaluated by experts in materials science and reviewed. Conflicting information
is commented upon and errors and inconsistencies removed wherever possible. It considers those, and only
those data, which are firmly established, comments on questionable findings and justifies re-interpretations
made by the authors of the evaluation reports.
In general, the approach used to discuss the phase relationships is to consider changes in state and phase
reactions which occur with decreasing temperature. This has influenced the terminology employed and is
reflected in the tables and the reaction schemes presented.
The system reports present concise descriptions and hence do not repeat in the text facts which can
clearly be read from the diagrams. For most purposes the use of the compendium is expected to be self-
sufficient. However, a detailed bibliography of all cited references is given to enable original sources of
information to be studied if required.
Structure of a System Report
The constitutional description of an alloy system consists of text and a table/diagram section which are
separated by the bibliography referring to the original literature (see Fig. 1). The tables and diagrams carry
the essential constitutional information and are commented on in the text if necessary.
Where published data allow, the following sections are provided in each report:
Literature Data
The opening text reviews briefly the status of knowledge published on the system and outlines the
experimental methods that have been applied. Furthermore, attention may be drawn to questions which are
still open or to cases where conclusions from the evaluation work modified the published phase diagram.
Binary Systems
Where binary systems are accepted from standard compilations reference is made to these compilations.
In other cases the accepted binary phase diagrams are reproduced for the convenience of the reader. The
selection of the binary systems used as a basis for the evaluation of the ternary system was at the discretion
of the assessor.
Landolt-Börnstein MSIT®
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XII Introduction
Heading
Literature Data
Binary Systems
Solid Phases
Pseudobinary Systems
Invariant Equilibria
Text
Liquidus, Solidus, Solvus Surfaces
Isothermal Sections
Temperature-Composition Sections
Thermodynamics
Notes on Materials Properties and Applications
Miscellaneous
References
Miscellaneous
Notes on Materials Properties and Applications
Thermodynamics
Temperature-Composition Sections
Tables and Isothermal Sections
diagrams
Liquidus, Solidus, Solvus Surfaces
Invariant Equilibria
Pseudobinary Systems
Solid Phases
Binary Systems
Fig. 1: Structure of a system report
Solid Phases
The tabular listing of solid phases incorporates knowledge of the phases which is necessary or helpful
for understanding the text and diagrams. Throughout a system report a unique phase name and abbreviation
is allocated to each phase.
Phases with the same formulae but different space lattices (e.g. allotropic transformation) are
distinguished by:
– small letters (h), high temperature modification (h > h )
2 1
(r), room temperature modification
(1), low temperature modification (l > l )
1 2
– Greek letters, e.g., (cid:74),(cid:74)'
– Roman numerals, e.g., (I) and (II) for different pressure modifications.
In the table “Solid Phases” ternary phases are denoted by * and different phases are separated by
horizontal lines.
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Intr o d u c t i o n XIII
Pseudobinary Systems
Pseudobinary (quasibinary) sections describe equilibria and can be read in the same way as binary diagrams.
The notation used in pseudobinary systems is the same as that of vertical sections, which are reported under
“Temperature – Composition Sections”.
Invariant Equilibria
The invariant equilibria of a system are listed in the table “Invariant Equilibria” and, where possible, are
described by a constitutional “Reaction Scheme” (Fig. 2).
The sequential numbering of invariant equilibria increases with decreasing temperature, one numbering
for all binaries together and one for the ternary system.
Equilibria notations are used to indicate the reactions by which phases will be
– decomposed (e- and E-type reactions)
– formed (p- and P-type reactions)
– transformed (U-type reactions)
For transition reactions the letter U (Übergangsreaktion) is used in order to reserve the letter T to denote
temperature. The letters d and D indicate degenerate equilibria which do not allow a distinction according
to the above classes.
Liquidus, Solidus, Solvus Surfaces
The phase equilibria are commonly shown in triangular coordinates which allow a reading of the
concentration of the constituents in at.%. In some cases mass% scaling is used for better data readability
(see Figs. 3 and 4).
In the polythermal projection of the liquidus surface, monovariant liquidus grooves separate phase
regions of primary crystallization and, where available, isothermal lines contour the liquidus surface (see
Fig. 3).
Isothermal Sections
Phase equilibria at constant temperatures are plotted in the form of isothermal sections (see Fig. 4).
Temperature – Composition Sections
Non-pseudobinary T-x sections (or vertical sections, isopleths, polythermal sections) show the phase
fields where generally the tie lines are not in the same plane as the section. The notation employed for the
latter (see Fig. 5) is the same as that used for binary and pseudobinary phase diagrams.
Thermodynamics
Experimental ternary data are reported in some system reports and reference to thermodynamic
modelling is made.
Notes on Materials Properties and Applications
Noteworthy physical and chemical materials properties and application areas are briefly reported if they
were given in the original constitutional and phase diagram literature.
Miscellaneous
In this section noteworthy features are reported which are not described in preceding paragraphs. These
include graphical data not covered by the general report format, such as lattice spacing – composition data,
p-T-x diagrams, etc.
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XIV Introduction
e
bl
a
reactiontemperatureof 261°C monovariantequilibrium stdown to lowtemperatures secondternaryeutecticreaction
Bi)
g e5+ (
Bi-A 1 Ag)
26 ((cid:156)
l
m
u
m
ctic reactionternary maxiature) Ag-Tl-Bi 294e(max)2L (Ag) + TlBi(cid:156)3 L + TlBi (Ag) + (Tl)(h)289U(cid:156)31 (Ag) + (Tl)(h) + TlBi289e(min)34L (Ag) + (Tl)(h)(cid:156) 207e(max)6L (Ag) + TlBi(cid:156)23 L (Ag)+(Bi)+TlBi197E(cid:156)231 Bi(Ag)+(Bi)+Tl23 L (Ag)+TlBi+TlBi188E(cid:156)3232 (Ag)+TlBi+TlBi323 (Tl)(h) TlBi + (Tl)(r),(Ag)144D(cid:156)31 (Ag)+(Tl)(r)+TlBi3 equation of eutectoidreaction at 144°C
uteper
first binary e(highest tem Tl-Bi 303e1 (Tl)(h)+TlBi(cid:156)3 202e7 (Bi)+TlBi(cid:156)23 192e8 TlBi+TlBi(cid:156)323 44e9h) TlBi+(Tl)(r)(cid:156)3 cheme
l l l 1 Tl)( on s
( cti
ond binaryectic reaction Ag-Tl 291e3l (Ag)+(Tl)(h)(cid:156) 234d1(Tl)(h) (Tl)(r),(Ag)(cid:156) Figure 2: Typical rea
ecut
se
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Intro d u c t i o n XV
C
Data / Grid: at.%
Axes: at.%
δ
p
1 700
20
80
500°C isotherm, temperature is usualy in °C
primaryγ-crystallization γ 500
40 400°C 60 liquidus groove to
decreasing temperatures
binary invariant 40
0
reaction 300 estimated 400°C isotherm
e
2 U e
ternary invariant 60 140
reaction
00 β(h)
3
80 400 α 300 E 400 500 700 20
limit of known region
A 20 40 60 80 B
Fig. 3: Hypothetical liquidus surface showing notation employed
C
Data / Grid: mass%
Axes: mass%
phase field notation
estimated phase boundary γ
20
80
γ+β(h)
40
60
phase boundary three phase field
(partially estimated)
experimental points
L+γ (occasionally reported)
60
40
tie line L+γ+β(h)
80 L β(h)
20
L+β(h)
L+α limit of known region
α
Al 20 40 60 80 B
Fig. 4: Hypothetical isothermal section showing notation employed
Landolt-Börnstein MSIT®
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XVI Introduction
750
L phase field notation
C 500
°
e,
ur
at
er
p
m
Te L+α 32.5% L+β(h) concentration of
abscissa element
250
L+α+β(h) β(h) temperature, °C
β(h) - high temperature
188 modification
α β(r) - room temperature
modification
α+β(h) β(r)
alloy composition
in at.%
0
A 80.00 60 40 20 A 0.00
B 0.00 B 80.00
C 20.00 Al, at.% C 20.00
Fig. 5: Hypothetical vertical section showing notation employed
References
The publications which form the bases of the assessments are listed in the following manner:
[1974Hay] Hayashi, M., Azakami, T., Kamed, M., “Effects of Third Elements on the Activity of Lead
in Liquid Copper Base Alloys” (in Japanese), Nippon Kogyo Kaishi, 90, 51-56 (1974) (Experimental,
Thermodyn., 16)
This paper, for example, whose title is given in English, is actually written in Japanese. It was published
in 1974 on pages 51- 56, volume 90 of Nippon Kogyo Kaishi, the Journal of the Mining and Metallurgical
Institute of Japan. It reports on experimental work that leads to thermodynamic data and it refers to 16 cross-
references.
Additional conventions used in citing are:
# to indicate the source of accepted phase diagrams
* to indicate key papers that significantly contributed to the understanding of the system.
Standard reference works given in the list “General References” are cited using their abbreviations and
are not included in the reference list of each individual system.
MSIT® Landolt-Börnstein
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Int r o d u c t i o n XVII
General References
[C.A.] Chemical Abstarts - pathways to published research in the world's journal and patent
literature - http://www.cas.org/
[Curr.Cont.] Current Contents - bibliographic multidisciplinary current awareness Web resource -
http://www.isinet.com/products/cap/ccc/
[E] Elliott, R.P., Constitution of Binary Alloys, First Supplement, McGraw-Hill, New York
(1965)
[G] Gmelin Handbook of Inorganic Chemistry, 8th ed., Springer-Verlag, Berlin
[H] Hansen, M. and Anderko, K., Constitution of Binary Alloys, McGraw-Hill, New York
(1958)
[L-B] Landolt-Boernstein, Numerical Data and Functional Relationships in Science and
Technology (New Series). Group 3 (Crystal and Solid State Physics), Vol. 6, Eckerlin, P.,
Kandler, H. and Stegherr, A., Structure Data of Elements and Intermetallic Phases (1971);
Vol. 7, Pies, W. and Weiss, A., Crystal Structure of Inorganic Compounds, Part c, Key
Elements: N, P, As, Sb, Bi, C (1979); Group 4: Macroscopic and Technical Properties of
Matter, Vol. 5, Predel, B., Phase Equilibria, Crystallographic and Thermodynamic Data of
Binary Alloys, Subvol. a: Ac-Au ... Au-Zr (1991); Springer-Verlag, Berlin.
[Mas] Massalski, T.B. (Ed.), Binary Alloy Phase Diagrams, ASM, Metals Park, Ohio (1986)
[Mas2] Massalski, T.B. (Ed.), Binary Alloy Phase Diagrams, 2nd edition, ASM International,
Metals Park, Ohio (1990)
[P] Pearson, W.B., A Handbook of Lattice Spacings and Structures of Metals and Alloys,
Pergamon Press, New York, Vol. 1 (1958), Vol. 2 (1967)
[S] Shunk, F.A., Constitution of Binary Alloys, Second Supplement, McGraw-Hill, New York
(1969)
[V-C] Villars, P. and Calvert, L.D., Pearson's Handbook of Crystallographic Data for
Intermetallic Phases, ASM, Metals Park, Ohio (1985)
[V-C2] Villars, P. and Calvert, L.D., Pearson's Handbook of Crystallographic Data for
Intermetallic Phases, 2nd edition, ASM, Metals Park, Ohio (1991)
Landolt-Börnstein MSIT®
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Al–Fe–V 1
Aluminium – Iron – Vanadium
Gautam Ghosh
Literature Data
[1960Gup] studied the effect of additions of Al on the stability of the (cid:41)-phase (FeV). They prepared a
number of alloys, using electrolytic grade elements, in an induction furnace under He atmosphere. The
alloys were homogenized at 1175°C for 72 h. Metallographic observations and X-ray diffraction were
performed to identify the phases. [1987Sok] and [1988Sok] reported the phase equilibria in the Al-rich
ternary alloys containing up to about 50 at.% Fe. The alloys were prepared using the metals of following
purity: 99.95 mass% Al, 99.95 mass% Fe and electrolytic V. A number of alloys were prepared by arc
melting under Ar followed by homogenization at 500°C in evacuated silica capsules. The V-rich alloys (0to
75 at.% Al) were heat treated for 1800 h at 1000°C followed by 600 h at 500°C, whereas Al-rich alloys (75
to 100 at.% Al) were annealed at 500°C for 1430 h [1988Sok]. The phase analysis was performed by means
of microstructural, thermal analysis, microhardness and X-ray diffraction techniques. Apart from
conventional casting, a number of ternary alloys were also subjected to rapid solidification by melt-spinning
which were subsequently annealed at 250 and 450°C for 50 h. An additional rapidly quenched alloy was
investigated by Mössbauer spectroscopy [1989Sok]. These results were assessed by [1992Gho] and
[1992Rag].
Recent experimental results are primarily related to phase separations [1989Zha, 1989Koz, 1993Miy,
1994Koz] and bcc-based ordering in Fe-rich alloys [1983Bus, 1985Okp, 1995Ant, 1997Nis1, 1997Nis2,
2001Nis1, 2001Nis2]. An update summarizing some of these results has been reported by [2002Rag].
Binary Systems
The Al-Fe and Al-V binary phase diagrams are accepted from [2003Pis] and [2003Sch], respectively. The
Al-Fe phase diagram has undergone slight modification due to recently established congruent melting
behavior of the Fe Al phase [1986Len]. The Fe-V phase diagram is accepted from [1982Kub], which has
4 13
also been adopted in [Mas].
Solid Phases
The maximum equilibrium solid solubilities of V and Fe in (Al) are about 0.3 at.% at 660.4°C [1989Mur]
and 0.03 at.% at 652°C [1982Kub], respectively. However, by rapid solidification, the corresponding solid
solubilities can be enhanced up to about 1.25 at.% V and 4.4 at.% Fe [1976Mon] and in the ternary regime,
the solid solubility can be up to 0.5 at.% V and 2 at.% Fe [1987Sok]. The lattice parameter of supersaturated
(Al) containing about 4.4 at.% Fe is about 401.2 pm [1976Mon]. Also, the lattice parameter of (Al)
decreases linearly to 404.2 pm at 1.2 at.% V [1976Mon].
The substitution of Fe by V in Fe Al increases both the D0 (Fe Al) (cid:156)B2 (FeAl) and the B2 (FeAl) (cid:156)A2
3 3 3
((cid:5)Fe) transition temperatures [1969Bul]. Recently, the effect of V on the D0 (cid:156) B2 ordering of Fe Al has
3 3
been determined by several investigators [1997Nis1, 1997Nis2, 2001Nis1, 2001Nis2]. These results are
summarized in Fig. 1. The D0 (cid:156) B2 temperatures reported by [1969Bul] differ significantly from those of
3
Nishino and co-workers, as a result the data of [1969Bul] are not considered in Fig. 1.
Along the Fe Al-V Al section, solid solutions (Fe V ) Al have been prepared [2003Kaw1]. The D0
3 3 1-x x 3 3
lattice of Fe Al (x = 0) has three sublattices labeled Al (4 sites), Fe (4 sites) and Fe (8 sites). V has a strong
3 I II
tendency to occupy the Fe sublattice as shown by X-ray absorption fine-structure [1997Nis1], and this
I
leads to the formation of Heusler phase at the ideal composition of VFe Al [1976Vla, 1983Bus, 1985Okp,
2
1997Nis1, 1997Nis2, 2001Nis1, 2001Nis2]. While the addition of V in Fe Al increases D0 (cid:156) B2 ordering
3 3
temperature, the Curie temperature of D0 decreases monotonically [2001Kan]. This is shown in Fig. 2.
3
Another consequence of substitution Fe by V is the decrease of lattice parameter of Fe Al down to a
3
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2 Al–Fe–V
minimum at the ideal Heusler composition of VFe Al beyond which it increases [2001Nis1, 2001Nis2].
2
This behavior shown in Fig. 3.
[1969Bul] also reported the D0 (cid:156) B2 and B2 (cid:156) A2 ordering temperatures along Fe Al-VFe section, both
3 3 3
showing increasing trend as V is substituted for Al as shown in Fig. 4. However, in view of the above
mentioned discrepancy, further measurements are needed to verify the results of [1969Bul].
As expected, V also increases D0 (cid:156) B2 ordering temperature of other Al-Fe alloys in the vicinity of Fe Al.
3 3
For example, [1995Ant] prepared three alloys VFe Al , V Fe Al and V Fe Al and measured the
73 26 2 72 26 4 70 26
ordering temperature using DTA. The D0 (cid:156) B2 temperature transition of these alloys are 585, 624 and
3
695°C, respectively.
[1997And] determined site occupancy of V in V Fe Al ((cid:5) ) by ALCHEMI (Atom Location by
5 50 45 1
CHanneling Enhanced MIcroanalysis) in TEM. [1997And] observed that about 80% of the “Al-site” is
occupied by V, and the residual “Fe-site” is attributed to the kinetics of site-equilibrium mechanism.
The Fe Al phase can dissolve about 5 at.% V at 500°C [1987Sok] and about 2 at.% V at room temperature
4 13
[1981Yin]. At 500°C, the VAl , V Al , V Al and V Al phases can dissolve up to about 6.5, 2.0, 1.7
3 4 23 7 45 2 21
and 4.5 at.% Fe, respectively [1987Sok]. The V solubilities in Fe Al , FeAl and FeAl were reported to be
2 5 2
about 3, 1.7 and 10 at.% V, respectively [1988Sok]. However, [2000Sah] uses, in the Al-rich corner at
475°C, a diagram in which V Al dissolves up to 4 at%Fe and Fe Al dissolves up to 8at.% V.
4 23 4 13
In contrast to the results of [1987Sok], Skinner et al. [1988Ski] reported that melt-spinning of Al-rich alloys
containing up to 16 at.% Fe and 10 at.% V gives rise to a quasicrystalline icosahedral phase. Also, [1988Ski]
suggested that the lattice parameter of such an icosahedral phase is dependent on the Fe:V ratio in the alloy.
Rapidly quenched alloys of the compositions 94Al-6Fe (at.%) and 95.3Al-4Fe-0.7V (at.%), which
consisted of (Al) + slight amounts of FeAl were investigated by Mössbauer spectroscopy. Two kinds of
6
coordination of Fe atoms in the Al lattice, a symmetric and an asymmetric one, were observed in the V
containing alloy. In contrast to this result the Al-Fe alloy had shown only one kind of coordination
[1989Sok]. The details of the crystal structures and lattice parameters of the solid phases are listed
inTable1.
Isothermal Sections
[1960Gup] reported the phase boundaries involving (cid:41) and ((cid:5)Fe) phases in the form of a partial isotherm at
1175°C. Al is a strong (cid:41) phase destabilizer; about 0.5 at.% Al at 1175°C is reported to be sufficient to
suppress the (cid:41) phase completely. [1994Koz] prepared ribbons of Fe rich alloys by melt-spinning. The
samples were annealed at 500C for 240ks, and were examined in a transmission electron microscope.
Figure 5 shows the partial Al-Fe-V isothermal section at 500°C from [1987Sok] and [1988Sok]. It should
be mentioned that the Al-V binary phases VAl , VAl and VAl as designated by [1987Sok, 1988Sok],
6 7 11
correspond to V Al , V Al and V Al in the presently accepted Al-V phase diagram. [2000Sah]
4 23 7 45 2 21
presents, in the Al rich corner at 475°C a diagram in which the solubility of Fe in V Al is very low so that
2 21
Al may be in equilibrium with VAl and V Al phases, which contradicts the observations of [1987Sok,
10 7 45
1988Sok]. Figure 1 also includes the results of TEM analyses on Fe-rich samples annealed at 500°C
[1989Zha, 1994Koz]. Three types of phase separation sequences from the single phase regions of the (cid:5),(cid:5)
1
and (cid:5) phases into the (cid:5)+(cid:5) phase region have been distinguished [1989Zha]. [1987Sok] also reported the
2 1
phases obtained in the as-melt-spun condition as well as after annealing at 250 and 450°C for 50 h. Their
results are summarized in Table 2. It was noted that, except for the ternary alloy containing more than 16.5
at.% Fe and 3.6 at.% V which was annealed at 450°C for 50 h, equilibrium was not reached in the rest of
the alloys after the annealing treatments used by the authors. For example, after annealing the binary Al-V
and Al-Fe melt-spun alloys at both 250 and 450°C, the authors obtained (Al+VAl +V Al ) and
3 2 21
(Al+Fe Al +FeAl ) phases, respectively. In the latter case, FeAl represents a metastable phase.
4 13 6 6
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Al–Fe–V 3
Thermodynamics
[2003Kaw2] measured various thermophysical (dilatability, compressibility) and thermochemical
properties of VFe Al, and proposes, for the heat capacity, the following expression:
2
C /J(cid:35)mol-1(cid:35)K-1 = 229 - 0.328 T + 2.50 (cid:35) 10-3T2 - 5.63 (cid:35)106T- 2.
p
[1994Koz] constructed the free energies of A2, B2 and D0 phases by a statistical approach employing
3
Bragg-Williams-Gorsky approximation. They considered both atomic and magnetic interaction energies up
to second nearest neighbor. Based on the model description of free energies, they calculated isothermal
section at 500°C which is good agreement with the experimentally observed microstructures of Fe-rich
alloys.
Notes on Materials Properties and Applications
Magnetic and electrical properties of V Fe Al alloys have been studied extensively [1985Okp,
1-x 2+x
1997Nis1, 1997Nis2, 1998Kat, 1998Weh, 2000Kat, 2000Zar, 2001Fen, 2001Han, 2001Kan, 2001Lue,
2001Mak, 2001Nis1, 2001Nis2, 2001Sum, 2003Kaw1]. An important finding is that VFe Al is nonmetallic
2
with respect to transport properties while it is metallic with respect to its thermodynamic properties. For
example, [1997Nis2] observed an anomalous negative temperature dependence of electrical resistivity such
that it behaves almost like a semiconductor. This is despite the fact that it has a large density of states at the
Fermi level as revealed by the photoemission valence-band spectra. VFe Al is non-magnetic semimetal
2
with a sharp pseudogap at the Fermi level [2000Kat]. It has been reported that a strong hybridization of Fe-
and V-3d states causes a broadening of the d-states and their shift to the higher binding energy. As a result
long-range magnetic order disappears and a narrow energy gap near the Fermi level is formed [2000Zar].
The unusual electron transport is mainly attributed to the effect of strong spin fluctuations, in addition to the
existence of very low carrier concentrations [2000Kat].
[1962Min] studied the effect of V addition on the properties of Fe Al. Addition of V increases hardness,
3
electrical resistivity and also improves the high temperature mechanical properties. [2001Nis1] reported the
mechanical properties of the (V Fe ) Al alloys. In the composition range 0 (cid:6) x (cid:6) 0.38, the room
x 1-x 3
temperature yield stress exhibits a double-well behavior starting from 550MPa for Fe Al with a first
3
minimum at 150MPa for x= 0.02, a maximum at 300MPa for x= 0.15 and a second minimum at 150MPa
forx = 0.333 corresponding to the composition VFe Al. Furthermore, [2001Nis1] observed a correlation
2
between the yield stress peak at higher temperature and the loss of D0 order. [2000Ino] reported a
3
significant increase in strength of rapidly solidified Al-Fe-V alloys containing nano-quasicrystalline phase.
Miscellaneous
From a preliminary investigation of the section Fe Al -V Al , a eutectic reaction was claimed to exist at
4 13 2 21
~610°C with an invariant composition at ~83 at.% Al [1988Sok].
References
[1960Gup] Gupta, K.P., Rajan, N.S., Beck, P.A., “Effect of Si and Al on the Stability of Certain (cid:41)
Phases”, Trans. Met. Soc. AIME, 218, 617-624 (1960) (Equi. Diagram, Experimental,
#,*,18)
[1962Min] Mints, R.S., Samsonova, N.N., Malkov, Y. S., “The Effects of Elements of Group V in the
Periodic System (V, Nb, Ta) on the Properties of Fe Al” (in Russian), Dop. Akad. Nauk
3
Ukrain. RSR,144, 1324-1327 (1962) (Experimental, 1)
[1969Bul] Bulycheva, Z.N., Svezhova, S.I., Kondrat’ev, V.K., “Change in the Ordering Temperature
of Fe Al on Adding a Third Element” (in Russian), Ukrain. Fiz. Zhur., 14, 1706-1708
3
(1969) (Crys. Structure, Experimental, 5)
[1976Mon] Mondolfo, L.F., “Aluminum-Vanadium System”, in “Aluminium Alloys: Structure and
Properties”, Butterworths, London, 392-394 (1976) (Review, 46)
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