J. GONDRO et al.: INFLUENCE OF STRUCTURAL DEFECTS ON THE MAGNETIC PROPERTIES ...
559–564
INFLUENCE OF STRUCTURAL DEFECTS ON THE MAGNETIC
PROPERTIES OF MASSIVE AMORPHOUS Fe60Co10Mo2WxY8B20-x
(x = 1, 2) ALLOYS PRODUCED WITH THE INJECTION CASTING
METHOD
VPLIV STRUKTURNIH NAPAK NA MAGNETNE LASTNOSTI
MASIVNE AMORFNE ZLITINE Fe60Co10Mo2WxY8B20-x (x = 1, 2),
IZDELANE Z METODO LITJA Z VBRIZGAVANJEM
Joanna Gondro, Katarzyna B³och, Marcin Nabia³ek, Sebastian Garus
Institute of Physics, Faculty of Production Engineering and Materials Technology, Czestochowa University of Technology,
Al. Armii Krajowej 19, 42-200 Czestochowa, Poland
j.gondro@wp.pl
Prejem rokopisa – received: 2015-06-30; sprejem za objavo – accepted for publication: 2015-07-29
doi:10.17222/mit.2015.148
This paper presents the results of research pertaining to high-field magnetic properties, in relation to the theory of H.
Kronmüller. Studies were performed on bulk amorphous alloys featuring composition Fe60Co10Mo2WxY8B20-x (x = 1, 2).
Samples were produced in the form of plates with a thickness of 0.5 mm; they were prepared by injecting the molten alloy into a
water-cooled copper mould. The influence of structural defects on the magnetization process was investigated within high
magnetic fields known as the area of the approach to ferromagnetic saturation. For the investigated samples, the studies showed
that, in the process of magnetization in high magnetic fields, rotation of the magnetization vector was mainly due to the
presence of linear defects in the structure, i.e., quasidislocational dipoles. The density of quasidislocational dipoles in a sample
with an addition of 1 % W was nearly twice as high as that of an alternative alloy.
Keywords: bulk amorphous alloy, metallic glasses, high magnetic fields, magnetization, structural defects, relaxation
^lanek predstavlja rezultate raziskav, ki se nana{ajo na visokomagnetne lastnosti, v povezavi s teorijo H. Kronmüllerja. [tudije
so bile izvedene na masivni amorfni zlitini s sestavo Fe60Co10Mo2WxY8B20-x (x = 1, 2). Vzorci so bili izdelani v obliki plo{~ic
debeline 0,5 mm, izdelane z vbrizgavanjem staljene zlitine v vodno hlajeno bakreno kokilo. Preiskovan je bil vpliv napak v
strukturi na proces magnetizacije v visokomagnetnih poljih, poznanih kot podro~je pribli`ka k feromagnetnemu nasi~enju. Za
preiskovane vzorce so raziskave pokazale, da pri procesu magnetizacije v visoko magnetnih poljih pride do rotacije magnetnega
vektorja predvsem zaradi prisotnosti linearnih napak v strukturi: to so kvazidislokacijski dipoli. Gostota dislokacijskih dipolov v
vzorcu, z dodatkom 1 % W, je bila skoraj dvakrat vi{ja kot pa pri drugi zlitini.
Klju~ne besede: masivna amorfna zlitina, kovinska stekla, visokomagnetno polje, magnetizacija, napake v strukturi, relaksacija
1 INTRODUCTION
Within the past decade, a group of materials known
as šbulk amorphous alloys’ have been studied inten-
sely;1–4 This interest is associated with their excellent
soft-magnetic and mechanical properties, which facilitate
their application. The amorphous alloys can be classified
into two categories: classic (in the form of thin ribbons
with a thickness of up to 100 μm) and bulk amorphous
alloys (with a thickness greater than 100 μm). The bulk
amorphous alloys are characterised by properties, which
are very difficult or even impossible to achieve in the
classic, ribbon-shaped, amorphous alloys.5,6 The group of
bulk amorphous alloys includes: ribbons with a thick-
nesses of approximately 100 μm, plates and rods with
diameters of a few millimetres, and cores that can feature
complex shapes.7
Although the finished amorphous alloys are in the
solid state, the constituent particles are distributed in a
chaotic way; their configuration is closer to that of the
liquid state.8 These alloys are characterised by a lack of a
long-range order and they exist in a metastable state. If a
sufficient quantity of energy is delivered to these meta-
stable materials, the crystallisation process will be
activated; therefore, this value of energy is called the
activation energy. The barriers to their crystallisation,
during the rapid-quenching process from the liquid state
(104–106 K/s), are mainly their high viscosity and the
presence of inclusions within their volumes.
The bulk amorphous alloys consist of more than three
elements and they are based mostly on Pd, Zr, Ti, Al,
Mg, Fe or Cu. The group with the highest prospects for
applications is based on Fe. Given an appropriate com-
position of this type of alloy, it is possible to obtain a
material with a stable structure and excellent magnetic
properties – both hard and soft. These properties are
often determined by local stresses in the structure,
resulting from the existence of structural defects. In the
case of crystalline materials, these irregularities are point
and linear defects; their counterparts in the amorphous
Materiali in tehnologije / Materials and technology 50 (2016) 4, 559–564 559
UDK 67.017:669.018.25:621.74.04 ISSN 1580-2949
Original scientific article/Izvirni znanstveni ~lanek MTAEC9, 50(4)559(2016)
materials are free volumes and quasidislocational di-
poles.
Defects are usually the result of the production pro-
cess itself, being a by-product of the rapid solidification,
"freezing" the structure. The resulting free volumes faci-
litate short- and long-distance movement of the atoms
within the systems of atomic pairs.8,9 The free volumes
created in a relatively slow solidification process, below
the glass transition temperature, have the ability to create
cluster systems. These clusters are systems with a low
stability and, as a result of the atomic movement, they
disintegrate into simpler, two-dimensional systems called
quasidislocational dipoles.10,11 A direct observation of the
structural defects of an amorphous structure is very diffi-
cult; therefore, the indirect method is used. This method
involves observation and analysis of the initial magneti-
sation curve, according to the H. Kronmüller theorem.12
On the basis of the modified Brown micromagnetism
theorem13, H. Kronmüller showed that structural defects
in the ferromagnetic materials with soft magnetic proper-
ties are the source of internal stresses, causing a locally
inhomogeneous distribution of the magnetisation vector.
The presence of these stresses in an amorphous material
prevents the achievement of the state of ferromagnetic
saturation, even under the influence of a strong magnetic
field.12
The magnetisation of the amorphous alloys within
high magnetic fields, in the so-called "approach to the
ferromagnetic saturation" region, could be described
using the following Equation (1):9
	 	
	 	 	0 0
1 2
0
1 2
1
0
1
2
0
21M H M
a
H
a
H
a
Hs
( )
) ) )
/
/= − − −
⎡
⎣⎢
⎤
⎦⎥
+
+b H( ) /	 0
1 2
(1)
where:
Ms – spontaneous magnetization; μ0 – magnetic per-
meability of a vacuum; H – magnetic field; ai – direc-
tional coefficients of the linear fit (free volumes and
linear defects i = 1/2, 1, 2); b – directional coefficient of
the linear fit.
The b coefficient is calculated on the basis of the
spin-wave theorem and connected with the spin-wave
stiffness parameter (Dsp) with the following relation: 14–16
b g
D
k T g=
⎛
⎝
⎜
⎞
⎠
⎟354
1
40
3 2
1 2. ( )
/
/	 	 	B
sp
B Bπ
(2)
where:
μB – Bohr magneton, kB – Boltzmann constant, g – gyro-
magnetic coefficient, T – temperature.
The strongest influence on the stresses, connected
with the existence of free volumes, is observed for the
a1/2 coefficient:
a
H A
r
r
G V N
A
1 2
0
1 2 0
2
2 2
3
20
1
1
2
/
/)
( )
	
	
 
=
+
−
⎛
⎝
⎜ ⎞
⎠
⎟ ⋅
⋅
ex
s Δ
ex
s	 	0
1 2
0
1 2
1
M H
⎛
⎝
⎜
⎞
⎠
⎟
/
/( )
(3)
where:
N – volume density of point defects, V – volume
change caused by point defects, Aex – exchange constant,
r – Poisson number, G – transverse elasticity modulus, s
– saturation magnetostriction.
The elements a1/μ0H and a2/(μ0H)2 are connected with
the linear, elongated agglomerates of free volumes, in
which the internal stress field is equivalent to the field
created by linear dislocation dipoles with a width of Ddip,
the effective Burgers vector beff and the surface density of
N. The stresses related to these defects cause a
non-collinear distribution of the magnetic moments in
their vicinity:17
a
H
G
V
Nb
M
D
H
1
0
0
2
2 2
2
0
211 1
1
	
	

	

)
.
( ) )
=
−
s eff
s
dip (4)
This situation exists, when l DH dip
− <1 1, and lH is the
exchange distance given with the following equation:18,19
l
A
HMH
=
⎛
⎝
⎜
⎞
⎠
⎟
2
0
1 2
ex
s	
/
(5)
In the case where l DH dip
− >1 1, the dominant element
influencing the magnetisation process, according to
Equation (1), is a2/(μ0H)2; this is described with Equation
(6):
a
H
G
V
Nb
M
D
H
2
0
0
2
2 2
2
0
20 456 1
1
	
	

	

)
.
( ) )
=
−
s eff
s
dip (6)
In Equation (1), each separate element exerts a major
influence on the magnetisation process in the approach
to the ferromagnetic saturation region, in strictly defined
ranges of the magnetic field. Therefore, it is possible to
define the influence of structural defects, inherent in
amorphous materials, on the magnetisation process
within high magnetic fields. On the basis of "defined"
defects, their packing density within the alloy volume
can be calculated using Equations (3), (4) and (6).20
2 MATERIALS AND METHODS
In this paper, results of investigations are presented
for the samples obtained by injecting liquid alloy into a
water-cooled copper die under a protective atmosphere
of inert gas (Ar). The manufactured samples were in the
form of plates with an approximate width of 10 mm and
a thickness of 0.5 mm. The nominal compositions of the
investigated alloys, Fe60Co10Mo2WxY8B20-x (x = 1, 2),
were obtained by weighing high-purity (99.9 %) compo-
nents.
J. GONDRO et al.: INFLUENCE OF STRUCTURAL DEFECTS ON THE MAGNETIC PROPERTIES ...
560 Materiali in tehnologije / Materials and technology 50 (2016) 4, 559–564
The structure of the resulting alloys was investigated
by means of an X-ray diffractometer. The BRUKER
"ADVANCE D8" X-ray diffractometer was equipped
with a Cu-K radiation source. The samples were studied
within a 2 range of 30–120° with a measurement step
size of 0.02° and an exposure time of 5 s per step.
Measurements of magnetization were performed over
a magnetic field range of 0–2 T using a vibrating sample
magnetometer (VSM).
3 RESULTS AND DISCUSSION
X-ray diffraction (XRD) curves for the investigated
alloys are presented in Figure 1. These curves feature
only one broad maximum, as characteristic of amor-
phous materials.
Static hysteresis loops were found to exhibit shapes
typical for ferromagnetic materials, which exhibit soft
magnetic properties (Figure 2).
The value of the coercive field was obtained from an
analysis of the static hysteresis loops, being 8705.57
A/m for the Fe60Co10W1Mo2Y8B19 alloy and 4610.88 A/m
for Fe60Co10W2Mo2Y8B18 (Figure 3).
From an analysis of the magnetisation as a function
of magnetic-field induction curves, it was found that the
magnetisation process in the Fe60Co10W1Mo2Y8B19 alloy
(Figures 4 to 6), where the domain structure is not
J. GONDRO et al.: INFLUENCE OF STRUCTURAL DEFECTS ON THE MAGNETIC PROPERTIES ...
Materiali in tehnologije / Materials and technology 50 (2016) 4, 559–564 561
Figure 5: Curves of high-field magnetisation as a function of (μ0H)–1,
for a plate-shaped sample of Fe60Co10W1Mo2Y8B19 alloy
Slika 5: Krivulje visokopoljske magnetizacije kot funkcija (μ0H)–1 pri
plo{~atih vzorch iz zlitine Fe60Co10W1Mo2Y8B19
Figure 2: Static hysteresis loops obtained for the investigated alloys
Slika 2: Stati~ne histerezne zanke, dobljene pri preiskovanih zlitinah
Figure 1: X-ray diffraction patterns for powdered as-quenched sam-
ples: a) Fe60Co10W1Mo2Y8B19 and b) Fe60Co10W2Mo2Y8B18
Slika 1: Rentgenska difrakcija kaljenih vzorcev prahu:
a) Fe60Co10W1Mo2Y8B19 in b) Fe60Co10W2Mo2Y8B18
Figure 4: Curves of high-field magnetization as a function of (μ0H)–½,
for a plate-shaped sample of Fe60Co10W1Mo2Y8B19 alloy
Slika 4: Krivulje visokopoljske magnetizacije kot funkcija (μ0H)–½ pri
plo{~atih vzorch iz zlitine Fe60Co10W1Mo2Y8B19
Figure 3: Coercive filed obtained from the analysis of the static
hysteresis loops for the investigated alloys
Slika 3: Koercitivno polje, dobljeno iz analize stati~nih histereznih
zank pri preiskovanih zlitinah
present, is influenced by two types of defect: point
defects, indicated, in Figure 4, by the linear relationship
of magnetisation as a function of (μ0H)–1/2 over a mag-
netic field range of 0.039–35 T and linear defects (called
quasidislocational dipoles), indicated, in Figure 5, by the
linear relationship of magnetisation as a function of
(μ0H)–1) over a magnetic field range of 0.35–1.2 T. In a
strong magnetic field, i.e., greater than 1.2 T, a small
increase in the magnetisation is connected with the
dumping of thermally induced spin waves by the strong
magnetic field (Figure 6).
The high-field magnetisation curves for the
Fe60Co10W2Mo2Y8B18 alloy are presented in Figures 7 to
9. Similarly, in the case of this alloy, the magnetisation
process is connected with the rotation of magnetic
moments around the point defects (Figure 7) and linear
defects (Figure 8), for which the relationship l DH dip
− <1 1
was fulfilled. The further increase in the magnetisation is
J. GONDRO et al.: INFLUENCE OF STRUCTURAL DEFECTS ON THE MAGNETIC PROPERTIES ...
562 Materiali in tehnologije / Materials and technology 50 (2016) 4, 559–564
Table 1: Results of the analysis of magnetisation as a function of magnetic field to the powers of –½, –1 and ½; spin-wave stiffness parameter Dspf
and Ndip – density of quasidislocational dipoles
Tabela 1: Rezultati preizkusa magnetizacije kot funkcije magnetnega polja na potenco –½, –1 in ½; parametra vrtilno-valovne togosti Dspf in
gostote kvazidislokacijskih dipolov Ndip
Composition
a1/2
(T–1/2)
a1
(T–1)
b
(T–1/2)
Dspf
(meVnm2)
Ndip
(1016m–2)
Fe60Co10W1Mo2Y8B19 0.166 0.089 0.108 29 51
Fe60Co10W2Mo2Y8B18 0.611 0.040 0.085 34 30
Figure 9: Curves of high-field magnetisation as a function of (μ0H)–½,
for a plate-shaped sample of Fe60Co10W2Mo2Y8B18 alloy
Slika 9: Krivulje visokopoljske magnetizacije, kot funkcija (μ0H)–½
pri plo{~atih vzorch iz zlitine Fe60Co10W2Mo2Y8B18
Figure 7: Curves of high-field magnetisation as a function of (μ0H)½,
for a plate-shaped sample of Fe60Co10W2Mo2Y8B18 alloy
Slika 7: Krivulje visokopoljske magnetizacije, kot funkcija (μ0H)½ pri
plo{~atih vzorch iz zlitine Fe60Co10W2Mo2Y8B18
Figure 6: Curves of high-field magnetisation as a function of (μ0H)½,
for a plate-shaped sample of Fe60Co10W1Mo2Y8B19 alloy
Slika 6: Krivulje visokopoljske magnetizacije, kot funkcija (μ0H)½ pri
plo{~atih vzorch iz zlitine Fe60Co10W1Mo2Y8B19
Figure 8: Curves of high-field magnetisation as a function of (μ0H)–1,
for a plate-shaped sample of Fe60Co10W2Mo2Y8B18 alloy
Slika 8: Krivulje visokopoljske magnetizacije, kot funkcija (μ0H)–1
pri plo{~atih vzorch iz zlitine Fe60Co10W2Mo2Y8B18
related with the existence of the Holstein-Primakoff
paraprocess (Figure 9).21,22
The parameters obtained from the analysis of the
high-field magnetization curves, obtained for both
alloys, are presented in Table 1.
4 CONCLUSIONS
During the production process involving bulk
amorphous alloys, structural relaxations occur, leading to
a more stable structure. This process influences both
topological (TSRO) and chemical (CSRO) short-range
ordering. Changes in TSRO are irreversible and con-
nected with the decreases in the volume and redistribu-
tion of free volumes.23 As a result, the average distance
between the atoms decreases and this, in turn, causes an
increase in the atomic packing density.
On the basis of the obtained results of the current
investigations, it could be stated that the investigated
alloys are amorphous. The value of the coercivity for
Fe60Co10W2Mo2Y8B18 is half the value for the other alloy.
On the basis of the magnetisation studies, carried out
in strong magnetic fields, it was found that for both
alloys the magnetisation process was influenced by the
presence of point defects and quasidislocational dipoles.
Also, the dumping of thermally induced spin waves by
the magnetic field (Holstein-Primakoff paraprocess) has
an influence on the magnetisation process. In the case of
the Fe60Co10W2Mo2Y8B18 alloy, both the a1/2, and a1
coefficients are half the equivalent values found for the
Fe60Co10W1Mo2Y8B19 alloy. Also, the value of the den-
sity of the quasidislocational dipoles Ndip is almost
halved for the alloy with a higher tungsten content.
These values indicate a higher atomic packing density in
the Fe60Co10W2Mo2Y8B18 alloy. The analysis of the
high-field magnetisation curves facilitated the calcul-
ation of the spin-wave stiffness parameter, Dspf, which is
connected with the changes in the chemical and topo-
logical atomic ordering. The higher value of this para-
meter for the sample of the Fe60Co10W2Mo2Y8B18 alloy
indicates a high concentration of magnetic atoms in a
given volume and confirms that the alloy has a higher
atomic packing density.
On the basis of the performed investigations, it can be
stated that an addition of 1 % (by weight) of tungsten,
replacing boron, caused a decrease in the number of
defects present in the investigated material and an
increase in the value of the spin-wave stiffness parameter
Dspf. This indicates that, during the solidification process
of the Fe60Co10W2Mo2Y8B18 alloy, structural relaxations
caused more atoms to take locally ordered positions. In
turn, this led to a decrease in the size of free volumes and
an increase in the atomic packing density within the
structure.
5 REFERENCES
1 T. Thomas, M. R. J. Gibbs, Anisotropy and magnetostriction in
metallic glasses, Journal of Magnetism and Magnetic Materials, 103
(1992), 97–110, doi:10.1016/0304-8853(92)90242-G
2 K. Sobczyk, J. Œwierczek, J. Gondro, J. Zbroszczyk, W. Ciurzyñska,
J. Olszewski, P. Br¹giel, A. £ukiewska, J. Rz¹cki, M. Nabia³ek, Mi-
crostructure and some magnetic properties of bulk amorphous (Fe
0.61Co0.10Zr0.025Hf0.025Ti 0.02W0.02B0.20)100-xYx (x=0, 2, 3 or 4) alloys,
Journal of Magnetism and Magnetic Materials, 324 (2012), 540–549,
doi:10.1016/j.jmmm.2011.08.038
3 M. Hasiak, K. Sobczyk, J. Zbroszczyk, W. Ciurzyñska, J. Olszewski,
M. Nabia³ek, J. Kaleta, J. Œwierczek, A. £ukiewska, Some magnetic
properties of bulk amorphous Fe-Co-Zr-Hf-Ti-W-B-(Y) alloys, IEEE
Transactions on Magnetics, 11 (2008), 3879–3882, doi:10.1109/
TMAG.2008.2002248
4 A. Brand, Improving the validity of hyperfine field distributions from
magnetic alloys: Part I: Unpolarized source, Nuclear Instruments and
Methods in Physics Research Section B, B28 (1987), 398–416,
doi:10.1016/0168-583X(87)90182-0
5 M. Nabia³ek, Soft magnetic and microstructural investigation in
Fe-based amorphous alloy, Journal of Alloys and Compounds, 642
(2015), 98–103, doi:10.1016/j.jallcom.2015.03.250
6 J. Olszewski, J. Zbroszczyk, K. Sobczyk, W. Ciurzynska, P. Bragiel,
M. Nabialek, J. Œwierczek, A. £ukiewska, Thermal stability and
crystallization of iron and cobalt-based bulk amorphous alloys, Acta
Physica Polonica A, 114 (2008) 6, 1659–1666
7 A. Inoue, Bulk amorphous alloys with soft and hard magnetic
properties, Materials Science and Engineering A, A226–228 (1997),
357–363, doi:10.1016/S0921-5093(97)80049-4
8 H. Kronmüller, Micromagnetism and microstructure of amorphous
alloys (invited), Journal of Applied Physics, 52 (1981), 1859–1864,
doi:10.1063/1.329552
9 H. Kronmüller, Magnetization processes and the microstructure in
amorphous metals, Journal de Physique Colloques, 41 (1980) C8,
C8-618-C8-625, doi:10.1051/jphyscol:19808156. jpa-00220256
10 H. Kronmüller, J. Ulner, Micromagnetic theory of amorphous ferro-
magnets, Journal of Magnetism and Magnetic Materials, 6 (1977),
52-56, doi:10.1016/0304-8853(77)90073-7
11 K. B³och, M. Nabia³ek, The influence of heat treatment on irrever-
sible structural relaxation in bulk amorphous Fe61Co10Ti3Y6B20 alloy,
Acta Physica Polonica A, 127 (2015) 2, 442–444, doi:10.12693/
APhysPolA.127.442
12 H. Kronmüller, Micromagnetism in amorphous alloys, IEEE Tran-
sactions on Magnetics, 15 (1979) 5, 1218–1225, doi:10.1109/TMAG.
1979.1060343
13 W. F. Brown Jr., Micromagnetics, Interscience Tracts on Physics and
Astronomy, Interscience Publishers (John Wiley & Sons), New York,
London 1963
14 O. Kohmoto, High-field magnetization curves of amorphous alloys,
Journal of Applied Physics, 53 (1982), 7486–7490, doi:10.1063/
1.330121
15 M. Nabia³ek, P. Pietrusiewicz, M. Doœpia³, M. Szota, J. Gondro, K.
Gruszka, A. Dobrzañska-Danikiewicz, S. Walters, A. Bukowska,
Effect of manufacturing method on the magnetic properties and
formation of structural defects in Fe61Co10Y8Zr1B20 amorphous alloy,
Journal of Alloys and Compounds, 615 (2015), S56–S60,
doi:10.1016/j.jallcom.2013.12.236
16 M. Nabialek, M. Doœpia³, M. Szota, P. Pietrusiewicz, Influence of
Solidification Speed on Quality and Quantity of Structural Defects in
Fe61Co10Zr2.5Hf2.5Y2W2B20 Amorphous Alloy, Materials Science
Forum, 654–656 (2010), 1074–1077, doi:10.4028/www.scientific.
net/MSF.654-656.1074
17 M. Vázquez, W. Fernengel, H. Kronmüller, Approach to magnetic
saturation in rapidly quenched amorphous alloys, Physica Status
Solidi A, 115 (1989) 2, 547–553, doi:10.1002/pssa.2211150223
J. GONDRO et al.: INFLUENCE OF STRUCTURAL DEFECTS ON THE MAGNETIC PROPERTIES ...
Materiali in tehnologije / Materials and technology 50 (2016) 4, 559–564 563
18 M. Hischer, R. Reisser, R. Würschum, H. E. Schaefer, H. Kron-
müller, Magnetic after-effect and approach to ferromagnetic satu-
ration in nanocrystalline iron, Journal of Magnetism and Magnetic
Materials, 146 (1995), 117–122, doi:10.1016/0304-8853(94)01643-7
19 N. Lenge, H. Kronmüller, Low temperature magnetization of sput-
tered amorphous Fe-Ni-B films, Physica Status Solidi A, 95 (1986),
621–633, doi:10.1002/pssa.2210950232
20 P. Pietrusiewicz, K. B³och, M. Nabia³ek, S. Walters, Influence of 1 %
addition of Nb and W on the relaxation process in classical Fe-based
amorphous alloys, Acta Physica Polonica A, 127 (2015) 2, 397–399,
doi:10.12693/APhysPolA.127.397
21 T. Holstein, H. Primakoff, Field dependence of the intrinsic domain
magnetization of a ferromagnet, Physical Review Letters, 58 (1940)
12, 1098–1113, doi:10.1103/PhysRev.58.1098
22 K. B³och, M. Nabia³ek, Approach to ferromagnetic saturation for the
bulk amorphous alloy: (Fe0.61Co0.10Zr0.025Hf0.025Ti0.02W0.02B0.20)97Y3,
Acta Physica Polonica A, 127 (2015) 2, 413–414, doi:10.12693/
APhysPolA.127.413
23 F. F. Marzo, A. R. Pierna, M. M. Vega, Effect of irreversible
structural relaxation on the electrochemical behavior of
Fe78-xSi13B9Cr(x=3,4,7) amorphous alloys, Journal of Non-Crystalline
Solids, 329 (2003), 108–114, doi:10.1016/j.jnoncrysol.2003.08.022
J. GONDRO et al.: INFLUENCE OF STRUCTURAL DEFECTS ON THE MAGNETIC PROPERTIES ...
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