Liquid-quenched Alloys

369 Pages·1991·18.651 MB·English

by  S. Kobe, A. R. Ferchmin (auth.), H. P. J. Wijn (eds.)

Ref. p. 1881 6.1 Amorphous 3d-M alloys (M = 4d, 5d, or main group element) 1
6 Liquid-quenched alloys
6.1 Liquid-quenched and sputtered alloys of 3d elements
and main group elements
6.1.1 Introduction
6.1.1.1 General remarks
Recently, the development of new solidification techniques has made available a variety of new materials with
composition ranges unattainable in crystalline alloys. Amorphous metallic alloys can be obtained by rapid
solidification from the liquid state. Typical cooling rates are of the order of, or higher than, IO6 K/s. Existing and
possible applications of amorphous magnetic materials are in context with their soft magnetic properties,
sometimes in combination with high electrical resistivity, their production-inherent low thickness and
magnetomechanical properties. Magnetic cores with low losses and specifically designed hysteresis loops,
magnetic heads, magnetic sensors and other applications are developed and partly commercially used. For
application-addressed magnetic properties see sect. 7.1 in subvolume 111/19i.
This data compilation will concentrate on the intrinsic magnetic properties of amorphous alloys, i.e., their
susceptibility in the paramagnetic region, magnetic moments and saturation magnetization, phase diagrams and
transition temperatures of ferromagnetically ordered alloys as well as of those alloys with more complicated
magnetically ordered structures (e.g.a morphous spin glasses)N. onmagnetic properties are included if they are in
some respect related to the magnetic properties, e.g. crystallization temperature, density.
Out of scope are systemsc ontaining rare earth elements, e.g. transition metal (TM) - rare earth (R) alloys;
they are dealt with in sect. 6.2, and also such alloys containing TM, R and other elements, cf. also [88 H 21.
Data for amorphous alloys produced by methods other than the liquid-quenching or sputtering, e.g.
electrodeposition, evaporation, ion implantation, solid-state reaction, spark erosion, etc., are not included in this
chapter.
Further on, we do not deal with the diamagnetic properties of amorphous alloys, since the latter are closely
related to superconductivity.
For an introduction to the problems of amorphous magnetic alloys the following books and review articles
are recommended: [80 H 1,83 L 1,84 M 7,84 K $84 E I,87 0 11.A survey with an extensive bibliographical part
is given in [83 F 2, 86 K 31. r
6.1.1.2 Preparation methods
Widely used techniques for the production of amorphous materials are: splat cooling and melt spinning
[SS G 23. For research purposes small samples can be obtained by solidification of a liquid droplet in a piston-
and-anvil or two-piston device. Melt spinning technique permits the formation of continuous ribbons (e.g.,b y
quenching the molten alloy on a rotating copper wheel or betweentwo rotating cylinders). The ribbons are one
millimeter to several centimeters wide and 30. ..50 pm thick. Wider ribbons (up to 10.. .30 cm) can be produced by
the planar-flow-casting method.
Another method for the production of amorphous alloys is sputter deposition: the material of interest is
bombarded at the cathode with positive ions of a rare gas. Thereby the atoms of the target are released and
collected on a substrate at the anode. See [84 M 73 for a review, and also [88 W I].
The inclusion of sputtered thick amorphous samples, separated from the substrate or not, and, to some
extent, of sputtered films was dictated by the similarity in the values of the magnetic parameters of both groups of
amorphous alloys for the samec hemical composition, together with the wider range of alloy composition which
can be prepared in amorphous form by sputtering.
As most of the data compiled concern liquid-quenched amorphous alloys, this is not specially indicated in
the tables and figures, whereas the data for sputtered samples are identified as such.
Landolt-Bijmstein Kobe, Ferchmin
New Series III/l9h
2 6.1 Amorphous 3d-M alloys (M =4d, 5d, or main group element) [Ref. p. 188
6.1.1.3 Structure
It is hardly possible to specify the atomic structure of a noncrystalline solid as precisely as that of a crystal. An
amorphous alloy can be characterized by the absence of long-range order or periodicity’in the microscopic
structure. The range of the short-range order is about 10 A (1 nm). The local order in the neighbourhood of a
given atom may be noncrystalline (e.g.t he local atomic arrangement of icosahedral symmetry) or that of a nearly
crystalline equilibrium or nonequilibrium phase [87 0 1-JT. o decide whether a substance is amorphous or not,
X-ray, electron and neutron diffraction can be used. In contrast to crystalline materials, the diffraction pattern
consists of diffuse rings which sharpen as the materials transform, on heating, into polycrystalline phases
(sometimesb eginning with a quasicrystalline phase). However, it is not possible to distinguish an amorphous
structure from one that is crystalline on a scale of less than about 20 8, (2 nm) [84 M 7-JA. n example of a reduced
radial distribution function, which is related to the probability of finding an atom at some distance from a given
atom, is shown in Fig. 1 [82A 4, 84 E l] for Fe,,B,,.
600
nmm2
-300I
0.1 0.2 0.3 0.1 0.5 0.6 0.7 nm 0.8
r-
Fig. 1. Reduced radial distribution function 4rrr[e(r)-
e,-Ja s a function of distance r from an average origin
atom for Fe,,B,,. e(r): density of atomsa t distancer , eo:
averaged ensity [82A4,84El].
Systems with structures other than amorphous, which can also be obtained by rapid solidification or
sputtering, are not included in this data compilation. It concerns micro- and nanocrystalline materials and the
recently observed “quasicrystals” (systemsp ossessingn oncrystalline short-range order and quasiperiodic long-
range order) as well as mixed amorphous/crystalline systemsi n casesw here partial crystallinity has been found
by the authors. The magnetic properties of powdered systems generally differ from those of the ribbons and
depend on the details of the process of powder preparation. Because of the resulting spread in magnetic
properties they, too, are omitted.
An amorphous alloy is in a thermodynamically metastable state. Such a state cannot be as uniquely defined
as a crystalline stable state. There exists a multitude of possible amorphous structures with grossly different
atomic arrangements and it is claimed that at least two different amorphous phasesc an coexist 186Z 1,87 B 5-j.
The consequenceso f metastability for the presentation of data on magnetic and other properties are twofold:
(i) Firstly, liquid-quenched alloy samples of the same composition from different batches can presumably
have somewhat different thermal histories (in the case of amorphous alloys, mostly a different quenching rate)
leading. similarly to the situation in ordering or segregating crystalline alloys (cf. 171V 11, chapter 21, 5), to
different local configurations of magnetic atoms, in particular different numbers of magnetic neighbours of
magnetic atoms. A practical rule states that the magnetization data of liquid-quenched alloys of the same
Kobe, Ferchmin LandolbB6mstein
New Series IW19h
Ref. p. 1881 6.1 Amorphous 3d-M alloys (M = 4d, 5d, or main group element) 3
composition usually differ by no more than several percent. Whenever possible, a typical value is given together
with the upper and lower limit data. Quite different metastable states can be obtained by imposing well defined
external conditions during the quenching process,e .g. by applying strong external magnetic fields (see[ 87 E I]).
Such conditions are indicated by remarks.
(ii) On the other hand, a metastable state tends to transform continuously towards progressively more stable
states.T his process is driven by the annealing temperature and time, sometimes also by a magnetic field and is
accompanied by structural relaxation phenomena. Data on magnetic properties measured after structural
relaxation are given together with the annealing conditions. Starting from the as-prepared state the relaxation by
annealing leads mostly to a relief of stress induced during the preparation process.
For commercial amorphous alloys nominal compositions only are usually available. For a few other alloys
solely nominal compositions are available as well. Such cases,r epresenting an obvious source of uncertainty, are
indicated in the “remark” column and should serve for provisional orientation.
Another source of uncertainty in magnetic data stemsf rom the nonuniformity of the samples:a s a rule, due to
the conditions of preparation, a surface layer differs chemically and structurally from the bulk and the surfaces
can differ from each other as well [87 S 51.
6.1.1.4 How to find the data of a specific alloy in this chapter?
As a consequenceo f the preparation conditions there are more amorphous alloys than crystalline materials
with the same components. The following rules should help the reader to find a specific alloy.
In principle, the rules of order for the amorphous materials follow the system of Chemical Abstracts (CAS).
Because the alloys under consideration are transition-metal-based, these elements determine the ordering.
(i) First, all alloys with a single TM element are listed following their order in the respective row of the
Periodic Table (Ti, V, Cr, Mn, Fe, Co, Ni, Cu). The other elements are arranged with decreasing atomic
percentage (e.g. Fe,,Si,5B,,).
(ii) Next, for a given TM element (e.g.F e) the alloys are ordered alphabetically according to the first (i.e. the
most abundant) non-TM element (e.g.F eB, FeC, FeSi, . . .) . Alloys composed of the same elements are arranged
with increasing TM content (e.g.F e7aBz1,F e,,B,,, . . .) . If the composition range of an alloy has to be given, the
right place is before the alloy with the lowest TM concentration (e.g. Fe,,, - XB, (17 5 x 5 21), Fe,aBzl, . . .); less
precise formulae are placed before more precise ones.
(iii) Alloys with more than one non-TM element are arranged in alphabetical order immediately after the
alloys with only one non-TM element and so on (e.g. Fe,,B,,, Fe,,B,,Mo,, Fe,,B,,Mo,, Fe,,B,,Mo,,
FMWbSi5, WA7Nb5, %3bW@L . . .). Please note that entries are not given, so that e.g.
Fe,,B&3,, can be found only after the Fe-B alloys, whereas Fe,,Si,,B,, only after Fe-Si. Sometimesa given
composition range covers two formulae (e.g. Fe,,B,S-.$3i, with 12sx5 14 covers Fe,,B,,Si,, and
Fe,,Si,,B,,). The formula is then situated only at the first place in the materials table (in the above example,
before Fe,,B,,Si,,).
(iv) In a formula for alloys with two TM elements,i n general, the TM element with the higher atomic number
in the Periodic Table is inserted preceding the TM element with the lower number. In this connection we consider
Cu as a TM element. However, becausei t is usual in the literature to write e.g. Fe-Ni instead of Ni-Fe (and
Co-Ni instead of Ni-Co), we keep the place an alloy should have in the table according to the above rules, but
once the place is chosen, we write the alloy formula in priority order: Co, Fe, Ni, Cu. The ordering rule is
illustrated by the following example for some Ni-Mn and Ni-Fe alloys: Ni,,Mn,Zr,,, Fe,,Ni,,B,,,
Fe,,Ni,B,,.
(v) For alloys with three TM elements first the ordering principles for the respective alloys with two TM
elements are used and then the third TM element is added according to the Periodic Table order.
(vi) With respect to the non-TM element in a given alloy, the materials are inserted in the order of increasing
content of the sum of all TM elements. If this sum is equal for alloys with the same elements, the alloy with the
lower content of the first-written TM element is given first.
Examples for these rules are to be found in the list of materials (subsect.6 .1.2).
The reader is advised to start his search with the materials list for the following reasons: the information he
needsc an be included either in a table or in a figure. Moreover, it occurs that more than one alloy is contained in
one figure. Then the figure is placed according to the material which occurs first according to the foregoing rules.
Land&-Biirnstein Kobe, Ferchmin
New Series III/19h
Ref. p. 1881 6.1 Amorphous 3d-M alloys (M = 4d, 5d, or main group element) 3
composition usually differ by no more than several percent. Whenever possible, a typical value is given together
with the upper and lower limit data. Quite different metastable states can be obtained by imposing well defined
external conditions during the quenching process,e .g. by applying strong external magnetic fields (see[ 87 E I]).
Such conditions are indicated by remarks.
(ii) On the other hand, a metastable state tends to transform continuously towards progressively more stable
states.T his process is driven by the annealing temperature and time, sometimes also by a magnetic field and is
accompanied by structural relaxation phenomena. Data on magnetic properties measured after structural
relaxation are given together with the annealing conditions. Starting from the as-prepared state the relaxation by
annealing leads mostly to a relief of stress induced during the preparation process.
For commercial amorphous alloys nominal compositions only are usually available. For a few other alloys
solely nominal compositions are available as well. Such cases,r epresenting an obvious source of uncertainty, are
indicated in the “remark” column and should serve for provisional orientation.
Another source of uncertainty in magnetic data stemsf rom the nonuniformity of the samples:a s a rule, due to
the conditions of preparation, a surface layer differs chemically and structurally from the bulk and the surfaces
can differ from each other as well [87 S 51.
6.1.1.4 How to find the data of a specific alloy in this chapter?
As a consequenceo f the preparation conditions there are more amorphous alloys than crystalline materials
with the same components. The following rules should help the reader to find a specific alloy.
In principle, the rules of order for the amorphous materials follow the system of Chemical Abstracts (CAS).
Because the alloys under consideration are transition-metal-based, these elements determine the ordering.
(i) First, all alloys with a single TM element are listed following their order in the respective row of the
Periodic Table (Ti, V, Cr, Mn, Fe, Co, Ni, Cu). The other elements are arranged with decreasing atomic
percentage (e.g. Fe,,Si,5B,,).
(ii) Next, for a given TM element (e.g.F e) the alloys are ordered alphabetically according to the first (i.e. the
most abundant) non-TM element (e.g.F eB, FeC, FeSi, . . .) . Alloys composed of the same elements are arranged
with increasing TM content (e.g.F e7aBz1,F e,,B,,, . . .) . If the composition range of an alloy has to be given, the
right place is before the alloy with the lowest TM concentration (e.g. Fe,,, - XB, (17 5 x 5 21), Fe,aBzl, . . .); less
precise formulae are placed before more precise ones.
(iii) Alloys with more than one non-TM element are arranged in alphabetical order immediately after the
alloys with only one non-TM element and so on (e.g. Fe,,B,,, Fe,,B,,Mo,, Fe,,B,,Mo,, Fe,,B,,Mo,,
FMWbSi5, WA7Nb5, %3bW@L . . .). Please note that entries are not given, so that e.g.
Fe,,B&3,, can be found only after the Fe-B alloys, whereas Fe,,Si,,B,, only after Fe-Si. Sometimesa given
composition range covers two formulae (e.g. Fe,,B,S-.$3i, with 12sx5 14 covers Fe,,B,,Si,, and
Fe,,Si,,B,,). The formula is then situated only at the first place in the materials table (in the above example,
before Fe,,B,,Si,,).
(iv) In a formula for alloys with two TM elements,i n general, the TM element with the higher atomic number
in the Periodic Table is inserted preceding the TM element with the lower number. In this connection we consider
Cu as a TM element. However, becausei t is usual in the literature to write e.g. Fe-Ni instead of Ni-Fe (and
Co-Ni instead of Ni-Co), we keep the place an alloy should have in the table according to the above rules, but
once the place is chosen, we write the alloy formula in priority order: Co, Fe, Ni, Cu. The ordering rule is
illustrated by the following example for some Ni-Mn and Ni-Fe alloys: Ni,,Mn,Zr,,, Fe,,Ni,,B,,,
Fe,,Ni,B,,.
(v) For alloys with three TM elements first the ordering principles for the respective alloys with two TM
elements are used and then the third TM element is added according to the Periodic Table order.
(vi) With respect to the non-TM element in a given alloy, the materials are inserted in the order of increasing
content of the sum of all TM elements. If this sum is equal for alloys with the same elements, the alloy with the
lower content of the first-written TM element is given first.
Examples for these rules are to be found in the list of materials (subsect.6 .1.2).
The reader is advised to start his search with the materials list for the following reasons: the information he
needsc an be included either in a table or in a figure. Moreover, it occurs that more than one alloy is contained in
one figure. Then the figure is placed according to the material which occurs first according to the foregoing rules.
Land&-Biirnstein Kobe, Ferchmin
New Series III/19h
6.1.2 Materials and properties - guide
Composition Properties Figures Tables Composition Properties Figures Tables
range range
Cr alloys Mn 22
22.~4177~
Mn 22
24.JA17S.7
Cr-Ge
Mn-Al-Si
CflOO-,Gex Mn, 7A158Si25 8
Mn-Au-!3
Crd+e72
Mn,Au,,Si,, 9
Crdk4
Crdh Mn-B
%8Ges2 M%,B,, 2
Crs7Geb3 22
Cr-Pd-Ge 10
CrxPd82-xGe18 15x57 ti Mn5A8 22
CrPdGe - XPdGe)- ’ 4
vs. T 10
Cr-PdSi Mn-P-C
Cr,Pd,$i,, MwP&o 2
Cr,Pd,,Si,, 22
Cr,Pd,,Si,, 11
Cr.,Pd,,Si,, Mn-Pd-Ge
CrsPd,,Si,, Mn,Pd,,-,Ge,, 15x57 ti 12
MnPdGc
Cr,Pd,,Si,,
- XPdGe) - ’
Cr,Pd,,Si,, vs. T
Mn-Pd-Si
Mn alloys
Mn,Pd,,Si,, 0 2
Mn-Al Mn,Pd,,Si,, 0 2
MnxA400-, 15~x524 @(x) 7 Mn,Pd,,Si,, 0 2
MnlsA185 x&9 x.c T 5 Mn,Pd,,Si,, 0 2
vs. T
M&i
L,(T) (log scale) 6 Mn~oo-xS4 255x575 T W' 69
x'. 09 CgrP err 2
~(Tm4.2 w
Mn20Ah xac(T) (log scale) 6 vs. x
C8 2
NL
ew Serieand&Biim
s IIIIl9hstein

K
o
b
e
, F
e
r
c
h
m
in
Composition Properties Figures Tables Composition Properties Figures Tables
range range
Fe-B (continued) Fe-B-Be
Fea4B16 D 12 Fea2-,%d% 06x510 i&d4 88
critical exponents 20 T,(x) 89
4, as 21 O~x~lO jFctx) 90
Tc 22 a4 91
Tc 129 22 05x512 T,(x) 92
4 21 FeaoB14Be6 TC 22
To TX 22 hoBdN Tc 22
Tc(hAT &-a) 83 Fea2B12B% TC 22
Fe B 4 21 Fea2B14Be4 Tc 22
85.4 14.6
To TX 22 Fea2B16B% TC 22
Fe,.&, D 12 Fe-B-C
4, a, 21 FGb3 -,G 755x587 PFdX) 78
TC 22 Fe78B22 Xx O-lx- llO 44 57
F%.,B,,.a 4 21 FexB1oo--x--yCy 8O-S- x188, as, 4 vs. Y 93
TC 22 06y$9
Fea7B13 4,~s 21 Fe80B20-xG 45--x 512 BFC 94
To TX 22 Fe80%&o 21
Fe 81.5 B 12.5 4, 21 Fe80B20 Xx 2(X) 57
Tc 22 FeaoB12G D 12
%A2 F’Fe 21 FeaoBl G r,, TX 22
Tc 22 F%o’%.& D 12
Fe-B-Al FedhG D 12
Fe84B16-xAlx 05x53 o,, T,, TX vs. x 84 F%oBd% D 12
Fe84B,3A13 Tc 22 FeaoBl& D 12
‘%B&6 21
Fe-B-AI-Si
Fe 81.5B 13.5C 5 22
Fe,,B,,A16Si2 21
Fed%& 22
Fe-B-Au Fed&2 r, 21
Fe80-xB20Aux O~x<lO liFdX) 85 T,(x) 22
T,, TX vs. x 86 O~x~lO 44 95
Fe82-xB18Aux 21x56 AT, per at% Au 87 57
b6B20Au4 21 D 12
BFc
Fed, ,Au2 as. PFe 21 4, as 21
Tc 22
F%&C, 4 21
D 12 Fe-B-M0
22 (Fe,-,Mo.&B,, 05x50.18 cm 100
TC pDFFM. O(X) 101
Fe-B-C-M0 12
G 22 21
Feo.&oo.&o- 0s
B,oC,o D 12
D 12
Fe-B-C-P-Si
21
21 as
FeslB13.&l.J’~.~- 22
Tc
Sii.8 22
TC
Fe-B-C-Si %(T) 102
21
Fe,,B,C&, 0s D 12
22
FesoWW~ Tc as 21
Fe,,(B-C-Si)19 0, ternary 96 Tc 22
diagram 21
0s
Fe8d13.dCW~ Tc 22 D 12
Fes2B12.4C2.sSi2.~ 0s 21 Tc 22
Fes3B12(CW~ Tc 22 Fe,,-,B,,Mo, 2<_x 16_ AT, per at% MO 87
Fes3B14Cl.5%.5 Tc 22 D 12
Fe76%20M04
21
Fe-B-Ga Qs
FelOo-x-yBxGay 0~~~26, cs ternary 97 Tc 22
O<y<6 diagram D 12
Fe,,-,%,,Ga, 01-x (8 _ i)Fe(X) 98 Tc 22
T,, TX vs. x 99 Fe77.6B2&02.4 Tc 22
Tc 22 Fe7sB20M02 Q,,B s 21
Qs 21 METGLASTM Tc 22
Tc 22 2605A T,, T,vs. 103
Fes4B13Ga3 Tc 22 neutron dose
critical exponents 20
Fe-B-Ge D 12
FesoB20-,Ge, 05-x 41-5 PF.(X) 94 21
Tc 22 0s
Fesl.A3.4h D 12
Qs 21
F%2.5Bl~G%.s 22
Tc 22 Tc
FFee s833B-x1B21G7eG5e x o<_x <3- PTFe, , T,vs. x 9989 FFees8o0B%157MMo0~3 dTTcc /dx, 104 22
Fe-B-Hf-Si-Al Fe-B-Mo-Si
Fe71B12Hf9Si5A13 OFFS, Hf 21 Fe,,%,,Mo.$i, To TX 22
21
Fe n.&&f~.s- FFe, Hf
S&Al,
21
Fe,,BizHf&A13 BFs. Hf, ijFe
Composition Properties Figures Tables Composition Properties Figures Tables
range range
Fe-B-N Fe4bNb-Si
Fe2d%J%2 105 Fe,,B,,Nb,& T,, T, 22
Fe42B33N25 105 (Fe,-,Nb,),,B,2- 0~x~0.115 T,, TX 108
%J%.3~~ 105 I, 109
106 F~~~@b, ask 79sx<88 us, T, vs. x 107
105 B12Sisa-~
106 (Feo.go5Nb~.d~3- To T, 22
Fes6B12N2 105 B12%
106
Fe-B-P
Fe,,‘%d’, P.1 21
AT, per at% Nb 87 FexByP1~~--r--y 75<- x18- 3, Pat(Y) 110
101 oI;y<22 Tc (Y) III
FesoB,P20-. o<_x <2- 0 PFc(X) 112
D 12 FeeoBzo-.P. 05x520 94
21 WdLJ’~~ FxC) 22
9 Nb’ u= 22
Fe-B-P-M0
DC 12 (%.93 M%dm- D 12
21
B,d’,o 0% 21
FNbVUS 22 Tc 22
DC 12
21 Fe-B-Pd
pFe.Nb, u, 22 F+P2J% 4 21
4T c 104 21 Fes3-,Bl,Pd, 01- x52- BTFC,. TX vs. x 1II41 3
dTc/&,
21 FeslB17Pd2 4 21
BFc. Nb, us, 4 22 Tc 22
Tc
Feo.g6~~.d~4.~- D 12 Fe-EPt
B 15.5 BFe, Nbv Us 21 Fes2-.BlsR 25x56 AT,perat%Pt 87
Tc 22 Fes3-,B17Pt, 05x56 PFe 113
(Fe~.dJb~.d~~.~- D 12 T,, TX vs. x 114
B 15.5 21 %J%Pt3 21
22 FeslB17Pt2 21
Fe-B-Re B 20
W%0Re80-x 501-x- 580 PFe, 7-c vs. x 115 T&-a) 118
Fe-B-Rh To TX 22
0s 21
F%A7Rh3 dTCl&th 104
% 21
Fe-B-Ru To TX 22
%dG7Ru3 dTc/dx,, 104
Fe-B-Ru-Si To TX 22
Fe,,B,,Ru&& 0s 21 44 119
Fe,,B,,Ru,Si, 0s 21 At(x) 120
We(x) 121
Fe-B-SC
TFe(X) 94
Fe8Ao% Tc 22 21
PFe, as
Fe-B-Si 22
To TX
Fe,B,Si, x>-6 5,y,zs35 T, ternary 116 22
To TX
diagram 21
4
4 21 22
TC
TC 22 &&& To TX 22
4 21 FC-32 (China)
Tc 22 Fed%& 22
Tc 22 . Fe81BloSi9 12
To TX 22 Fe,lB13% 21
Tc 22 Fe81B15SL 21
21-x- 16 AT, per at% Si 87 Fe81B16Si3 22
as, 4 21 Fe81B16.5SL5 21
Tc. TX 22 Tc 22
Tc 22 TC 22
To TX 22 Tc 22
Tc, TX 22 0s 21
To TX 22 Tc 22
4 21 hdL3i~ 4 21
hdWi6 To TX 22
fls 21 FC-31 (China)
Tc 22 Rdh& 21
M-7 117 METGLASTM 22
Fe7Jh5% D 12 2605 S
Fe78B13Si9 4 21
METGLASTM To TX 22 0s 21
2605 S-2 TC 22
Tc 22
0s 21