Superconductivity
of
the Pla
tinurn
Metals
and
Their
Alloys
A
REVIEW SUMMARISING T H E PUBLISHED SCIENTIFIC
DATA
By
Ch.
J.
Raub
Forsrhungsinstitut fur Edelrnetalle und Metallrhernie, Schwabisrh Grnund, West German!
Continuing investigation 0.f superconductivity, particularly o~f platinum metal compounds, has resulted in a growing undwstanding o,f the phenomenon. Accumulating data contain some remarkable experi- mental results which in time must surely ,find both theoretical explana- tion and industrial application.
T h e electrical and magnetic behaviour of the platinum metals and their compounds has fascinated solid state chemists and physicists for many years. Together with iron, cobalt and nickel the platinum metals belong to Group
VIII of the Periodic Table, and one of the earliest problems was to consider why they did not show any magnetic ordering, in contrast to iron, cobalt and nickel. On the other hand, when in the form of solid solutions or com- pounds they exhibited very interesting mag- netic behaviour, for example localised moments and spin glass behaviour. The magnetic strengths of cobalt-platinum alloys even found industrial application.
With the discovery of “superconductivity” by Kammerlingh-Onnes and the hypothesis of
B. T. M a t t h i a s a n d o t h e r s t h a t
quently developed into specialised research areas of their own. Even now it is impossible to predict the T, or T, (T,= magnetic ordering temperature) of an alloy. Indirectly this work has led to new approaches in other areas, for example the growth and study of single crystals. Up to now superconductivity has found only limited application in high technology areas for example in magnets for fusion and atomic research at CERN and Culham, and for electrical motors and generators. However, one can expect that the platinum metal compounds discussed here, with their unique properties, will in time find applications which cannot be envisaged at present, perhaps especially for solid state devices.
It has been known for some time that three of the six platinum group metals in high purity superconductivity-that is the loss of any
electrical resistance below a critical temperature, T,- and ferromagnetism exclude each other even though they are based on similar phenomena, the investigation of the low temperature electrical and magnetic behaviour of the platinum metals and their compounds became of special interest.
In the course of this research many new and unexpected phenomena were discovered in p l a t i n u m m e t a l a l l o y s , n a m e l y
superconductivity of hydrides, a n d
superconductivity/ferro- or antiferromagnetism in ternary compounds, topics which subse-
Table I
Superconducting Transition Temperatures
(TJ of
SomeRE,T,Ge,,
Compounds(RE is Yttrium or Lutetium;
T is Ruthenium or Osmium)
3.9 - 3.7 Lu,Ru,Ge,, 2.3 - 2.2 3.6 - 3.1
form become superconducting, these being ruthenium, osmium and iridium. In addition, many years ago, it was predicted from investigations made of rhodium alloy systems that the element rhodium might also become a superconductor at a temperature around
0.2 mK ( I ) , and this has recently been
established (2, 3). T h e superconductivity of the individual metals will now be considered.
Ruthenium
The superconducting transition temperature of ruthenium has been placed between 0.40 and 0.509
k
0.002 K (4, 5 , 6). The generally accepted values for its superconducting properties are: transition temperatureT, = 0.49
t
0.01 5 K, critical fieldH, = 69 5 2 Oe, Debye temperature
O1,= 580K, and the coefficient of low temperature specific heat 1' = 2.8 mJ/moVK (7). The dependence of critical temperature on its atomic mass M (isotope effect) is relatively small. For powdered and arc furnace melted samples of Ru99 and RuIo4 it was reported that the critical temperature coincides within the accuracy of measurements (8) and similar results were obtained later (9, 10). Measure- ments made on samples with an average atomic mass
a
of 99.2, 1 0 1 . 1 and 103.9 in magnetic fields up to 70 Oe gave the dependence:T c - -M-l'R. At pressures up to 30,000 atmospheres the critical temperature is not affected by the applied pressure ( I I), while its volume dependence Gln(TJOD)/GlnV = - I 6 ( I 2).
Osmium
The critical temperature of osmium as given in the literature ranges from 0.4 to 0.7 I K ( I 3). An arc furnace melted sample of 99.9 per cent purity had a resistance ratio of pu/p27) = 0.4
and T, = 0.71 K, at a width of transition of 0.02 K (14). Today generally accepted values for the superconducting properties are
and y = 2.35 mJ/mol/K (7). Isotope effect measurements do not agree, even when apparently identical samples are checked ( I 0 , I 5). According to Geballe and Matthias T, = 0.66 & 0.03 K, H , = 70 Oe, O D = 500 K
( 1 0 ) osmium has no isotope effect, while Hein and Gibson ( I 5 ) found T , z M-".*. The critical field is 80.9 Oe when = 187.4, and 80.2 Oe when = I 92.0 ( I 5). At a pressure of 30,000
atm the critical temperature of osmium is reduced by 0.05 K ( I I). In a review paper con- sidering the influence of the purity of samples on their critical temperature it was shown that the sample with the highest resistance ratio, which was = 500, had T, = 0.638 K ( I 6).
Iridium
By suitable heat treatment in an arc melting furnace it has been possible to remove from iridium samples, by evaporation, ferromagnetic impurities such as iron, when a TL = 0. I 4 K is obtained for the iridium (17). However, for
samples containing 5 0 ppm of iron
T, = 0. I 0-0. I I K ( I 8). Iridium purified by electron beam melting until the total impurity content is below 1 0 ppm has a critical temperature curve with a mid point at
0. I I 25
t
0.005 K.Furthermore its transition curve is characterised by an uncommon hysteresis; the transition from the normal to the superconduct- ing state occurs discontinuously but from the superconducting to the normal state it is con- tinuous. Additionally, it is influenced by the applied magnetic field. The coherence length is 4.4 x Io-lcm, and the penetration depth 3.9 x 1 0 'cm. Small impurity concentrations reduce the critical temperature of iridium and make it a superconductor of the second kind. Accepted values are now: T, = 0.1 125 & 0.001 K, H,(T = 0 ) = 1 6
i
0.05 Oe,OD
= 425 K and1' = 3. I 9 mJ/mol/K ( I 3); the pressure depend- enceofT,is-(5.1
*
0.9) x ro-'K/atm(rg).Rhodium
rhodium as an element ( I ) . X-ray analysis suggested the samples were homogeneous, but microprobe investigations of the rhodium- iridium alloys showed some slight coring, but for the rhodium-osmium alloys the concentra- tion varied by up to 20 atomic per cent. In
order to avoid the introduction of impurities and segregation, the alloys had not been heat treated and therefore showed relatively broad transitions. T h e superconducting transitions for the rhodium-iridium alloys were spread over a width of I mK while for the rhodium-osmium alloys, at the higher temperatures, the spread was very wide and sometimes incomplete. However, as mentioned earlier, it was deduced from these results that rhodium would become a superconductor at a temperature of 0.2 x lo-) K, a temperature predicted to be "at least a decade away" ( I ) . With significantly improved refrigeration facilities it has recently been established that polycrystalline rliodium is in fact superconducting at a critical temperarure of 325 pK (2, 3).
Palladium and Platinum
Even extra purified palladium and platinum are not superconducting. The lowest test temperature published is 0.1 K (7, 1 3 , 2 0 ) but according to a private communication from A.
C. Mota neither palladium nor platinum are
superconducting, even if checked at
temperatures as low as I o x I o-) K.
Alloys of
Platinum Group Metals:
with
Hydrogen
T h e discovery of superconductivity in p a l l a d i u m - h y d r o g e n s a m p l e s , l o a d e d electrolytically up to H:Pd ratios >0.8, started an intensive investigation of binary and ternary palladium-hydrogen alloys with regard to superconductivity (21). By using ion- implantation techniques and low temperature electrolysis, H:Pd ratios
>
I .o were obtained with critical temperatures of 8.8 K for palladium-hydrogen and - I 0.7 K for palladium-deuterium samples (22). Ternary palladium-copper-hydrogen samples exhibited a maximum critical temperature at H:PdsrC U J ~ z 0.8 of about 17 K. The values in the
system palladium-silver-hydrogen are:
H:Pd7"Ag3" z 0.8 and T, z I 6 K and in the system palladium-gold-hydrogen they are: H:PdsrAuI6 =: 0.9 and T,= 1 3 . 6 K (23). In these alloys the maximum critical temperature shows up at lower H:Pd ratios and this effect is explained by the reduction of the critical temperature lessening "spin" fluctuations (24). Apparently the disappearance of the strong paramagnetism of palladium is a prerequisite for the occurrence of superconductivity, as has been shown earlier for palladium-molybdenum and palladium-tungsten solid solutions (24). Ion-implantation experiments on Pd I-~AI, and Pd I-xTix alloys (H:Pd
<
0. I 5 ) showed a reduc- tion in the maximum critical temperature with increasing aluminium and titanium concentra- tion (25, p. 236). Palladium with ion-implanted lithium, boron, carbon or nitrogen showed superconductivity only for the palladium-boron-hydrogen and palladium-carbon-
hydrogen alloys at 3.8 and 1.3 K. The lithium and nitrogen containing samples were not superconducting above 0.2 K (25, p. 237). The effect of replacing part of the palladium by nickel, platinum or rhodium and silver in ion- implanted and pressure loaded palladium- hydrogen and palladium-deuterium alloys has been considered (25, p. 243; 26, 27, 28). Up to
10 atomic per cent nickel suppresses the critical
temperature rather strongly, but platinum has little influence on critical temperature at con- centrations up to 25 atomic per cent (25, p.
There is no relationship between critical temperature, susceptibility and the coefficient of the low temperature specific heat for the rhodium-palladium-silver and nickel-palladium- platinum alloys investigated (25, p. 254).
T h e pressure coefficient of palladium- hydrogen alloys 61nTJ6P is -0.01 W a r (25, p.
For samples containing identical hydrogen and deuterium concentrations, the isotope effect results in a Tc,l)/Tc,H in the range I to 2.2 (29). In thin palladium films it was observed that the behaviour corresponds to that of bulk 253).
253).
palladium at thicknesses above 2000
A.
Films with thicknesses of 320A
exhibit no superconductivity at up to I K (30). In very fine palladium-hydrogen powder samples, produced by electrolytic co-deposition at -3o"C, which X-rays showed to be amorphous, no supercon- ductivity was observed above 1.9 K even if the pa1ladium:hydrogen ratio was varied (29), con- firming observations by Raub and Loebich (3 I ) .Alkaline Metals
None of the alloys of the platinum metals with lithium, sodium or potassium is superconducting above 2 K. This is valid for the solid solutions, as well as for the compounds at present known (7, 13, 32). Electrolytically loading palladium-lithium solid solution samples with hydrogen did not produce superconductivity above I .9 K (33).
Copper, Cold and Silver
None of the alloys of the platinum metals with copper, gold or silver is superconducting above 2 K. Rhodium-copper samples, in the solid solution range, are not superconducting down to 0.3 K (33). The ternary phase Ag2Pd3S, A I 3-type, a = 7.235 A, has Tc = I . I 3 K (34).
Group
I I
Elements
Barium, Beryllium, Calcium. Magnesium. and Strontium
Beryllium forms superconducting phases with four of the platinum metals but not with palladium and platinum; however sometimes it
is unclear to which phases superconductivity must be attributed (7, 13, 35). Be13Ru and Be2Ru show critical temperatures of I .3 and 1.35 K, respectively (35). Of the many beryllium-rhodium compounds only Be2Rh is superconducting at I .37 K (35). The transition temperatures of the beryllium compounds increase with beryllium content: for BerOs T , = 9.2, for Be20s T,= 3.07 and for BeoscOsoo~ T,= 0.57 K (7, 35). Among the beryllium phases with iridium only Bedr is superconducting, with T,= 1.5 K (35). The transition temperatures of the calcium com- pounds with Cr 5-type Laves phase structure
are for CaRh2 T, = 6.4 and for CaIr2 T, = 4 to 6. I 5 K; for the corresponding strontium and barium phases SrRh2 T, = 6.2, SrIr2
- I c
= 5.7,SrPt? T, = 0.7, and BaRhz T, = 6.0 K (36, 37).
Cadmium, Mercury and Zinc
None of these three are known to form superconducting phases with the platinum metals, which is at least partially explained by the problems concerned with the formation of superconducting shields and the experimental difficulties due t o the wide range of vapour pressures among the components (37).
Croup
I11
Elements
:I
I
u in i n i 11 m, Horon. (;a II
iu m. I nd i uniand Thalliuni
The compound BlRu is superconducting at 2.58 (7) and B2Ru at 1.6 K (38,39). None of the binary borides of platinum or palladium shows superconductivity above I .2 K (32, 39).
Superconducting ternary palladium-hydrogen- boron alloys can be prepared by ion- implantation techniques (25). OsB2 has a critical
temperature of about 2 K (39), but
superconducting binary iridium borides are
unknown. Ternary iridium-boron phases
having an orthorhombic structure are B21rMo2 with T, = 1.25, B21rI.2VI.X T,= 1.25 and B21rV2 T, = I . I 2 K. The corresponding ruthenium compounds are BzRuMo2 with T,= 2.48 to
TL = 3.32 to 3.42 K (39). The hexagonal phases
Bao67PtlB2, Sr0.67Pt3B2 and Ca067Pt$2 are superconductors below 5.6, 2.7 and 1.57 K, respectively (40).
Among osmium-aluminium phases OsAl and Os4Alli become superconducting at 0.9 and 3.3 K, respectively (32,41). The critical temperature of 5.9 K for OsA13 is probably the same for Os4Al I l (4 I , 42).
2.57, B ~ R u W I 5 T, = 2.83 to 3.28, BzRuWz
Lanthanum. Srandium.
I
ttrium and the Hare Earth I\.It.tals1 4 1 - -
\
0
0 0
Y
o
I . . . , . r . . T .
U Ce Pr Nd Rn Srn E u Gd Tb Dy Ho E r Trn Yb Lu RARE EARTH ELEMENT
I i g . I Superronducting critical (Tc).
YVPel ( T h ) and Curie (T,,,) temperatures of HERh J5 I compounds, after rdt.renre ( * 5 5 ) - 0 ‘1’#,
mT,,,.
oT1I 3, 32,43,44,45,46,47). It was first shown by V. B. Compton and B. T. Matthias (48) that the C14- and CIS-type Laves phases of the platinum metals and the rare earths, and the Group 111 metals without free 4f electrons, exhibit superconductivity, while those with free 4f electrons, that is the elements from praseodymium to ytterbium exhibit ferromag- netism, an exception being CeRuz (C I ytype)
for which T,= 4.9 K (32, 48). The
simultaneous occurrence of superconductivity
and ferromagnetism in pseudo-binary systems has been investigated in a series of papers on C I 5-type YOs2-GdOs2, CeRuz-PrRu2 and CeRu2-GdRuz alloys (44-5 I).
Among the C I S phases of the noble metals with Group I11 elements, CeRuz and L a o s z exhibit the highest critical temperature, this being 6.5 K. Among C I ~ - t y p e phases they are YOSZ and LUOSZ with T,=4.7 and 3.49K, respectively. Among the Os2-rare earth com- pounds the Curie temperature is highest at OsGd2 (80 K). It drops down evenly to near o K at OSLUZ (46). T h e magnetic moments show two maxima at RuzPr and RuzDy and a minimum for europium compounds. This behaviour is equalled by that of the iridium and osmium rare earth C I 5-type phases (52).
In the system iridium-yttrium a maximum critical temperature of 0.5 K is found at about
50 atomic per cent. Most likely this is caused by shields of Ir3Y or Ir4Y. IrZY, is superconducting at 1.61 K and Ir2Y is superconducting in its homogeneity range, from 0.88 to 2. I 8 K. The composition of the superconducting phase richest in iridium is near Ir4Y (53). Nevertheless the behaviour is still somewhat unclear. Scandium-rich r h o d i u m alloys show superconductivity beginning ( p a r t i a l superconductivity) near 0.9 K (53).
In the systems consisting of platinum metals
with yttrium, scandium and lanthanum
superconductivity is explained by T. H. Geballe
Fig. 2 The primitive tetragonal crystal structure of the rare earth rhodium borides RERh.&with the outline of the unit cell indicated by broken lines. For clarity, the R h a I - c l u s t e r s are not drawn t o scale, after reference (64)
as most likely being of a filamentary nature (54). In the lanthanum-rhodium system approximately I per cent lanthanum in the melt is enough to make the solidified alloy appear fully superconducting. Even 0.1 per cent lanthanum gave a smeared transition (54).
Ternary Compounds
of
the
Type
RERh
J3
IThe ternary borides of the rare earth metals belong to a group of new superconducting com-
pounds, which was discovered by
B. T. Matthias and collaborators in 1977 (55). The compounds are tetragonal in structure, of the CeCo4B4 type (55, 56). As with the binary Cr 5 phases of the rare earths, elements with an
unfilled 4f shell, namely neodymium,
samarium, erbium, thulium and lutetium, show superconductivity; those with the filled shell, that is gadolinium, terbium, dysprosium and holmium are ferromagnetic (57). Up to now, it is impossible to prepare compounds with lanthanum, cerium, europium and ytterbium. All superconducting phases exhibit long range magnetic ordering at a temperature T, which is below t h e superconducting transition temperature T,. T h e superconducting transi- tion temperatures and the ferromagnetic Curie temperatures of the RERh4B4 compounds are shown in Figure I (55).
A wide range of pseudo-binary compounds of these phases was investigated for the interaction between superconductivity, magnetic ordering and “crystalline field splitting”, for example Erl-,Ho,Rh4B4 (58) and Sml-,Er, Rh4B4 (55).
Osmium compounds T, 2 0.1 K Ruthenium compounds
Ce,Os,Ge,, 6 . 1 Ce,Ru,Ge,,
Pr,Os,Ge,, 1 6 . 0 Pr,Ru,Ge,,
Nd,Os,Ge,, 1.9
Eu,Os,Ge,, 10.1
DySOs,Ge
,
,
2.1Tb,Os,Ge,, 14.1
Er,Os,Ge,, 1.9 Er,Ru,Ge,,
Rhodium can be replaced at least partially by ruthenium (59) or iridium (60). For the phase
Ho(Ir0 6Rho 4)JB, co-existence between superconductivity and antiferromagnetism was observed, the Nee1 temperature being higher than the critical temperature (60). Crystallogra- phic, magnetic and superconducting properties of the system Y Rh 4B4-Lu Rh +B 4-ThRh +B lead the authors to conclude that the lattice volume has relatively little influence on the electronic density of states.
Several reviews of the numerous investiga- tions carried out on ternary borides have already been presented (59-64). The structure of RERhJB4 is shown in Figure 2 (64).
T,+0.1 K
6.7 14.2
Group
IV
Elements
G e r m a n i u m . Lead, Silicon a n d ‘Tin
Among these compounds the only
superconductors are PdSi, where T, = 0.93 K;
PtSi, T,= 0.8 K; Rh5Ge3, ? I c = 2.12 K (7, 13,
32); together with RhGe, T c = 0.96 K (65); IrGe, T,= 4.7 K (66); PtGe, T,= 0.4 K (32);
and RhSn2, T,= 0.60 K (67). Ternary
superconductors are the ruthenium and osmium germanides Y1RuGel3 and Y3OsGe13, having a Yb1Rh4Sn, type structure, see Tables I and I1 (68, 69, 70). Ternary silicides and ger- manides with ruthenium, rhodium and osmium and the rare earths, of the S C + ~ O $ ~ I O type of structure, show a similar behaviour (68, 69, 70). The superconducting transition temperatures of the R E I T J G c 1 3 phases are shown in Table I
and the magnetic ordering temperatures in Table I1 (68,69, 70).
Table II
Table Ill
S u p e r c o n d u c t i n g T r a n s i t i o n T e m p e r a t u r e s (T,.) a n d Magnetic
O r d e r i n g T e m p e r a t u r e s
(T",)
of Sc$o &Si,,,
T y p e C o m p o u n d sCorn po u nd
Sc,Co,Si,,
Sc,Rh,Si,,
Sc,l r,Si
Y,lr,Si ,o
Lu,lr,Si,,
Tm ,I r,Si
,
Er51r4Silo
Ho,l r,Si
Dy51r,Sil,
Y51r4Silo
Y5°s4Ge10
~~
TCK
5.0 -4.8
8.54 - 8.45
8.46 - 8.38
3.0 -2.3
3.76 - 3.72
2.62 - 2.58
8.68 - 8.41
The superconducting transition and mag- netic ordering temperatures of Sc&o4Si lo type
phases, having a primitive tetragonal lattice of a new structure type, are listed in Table 111 (68,
Similar superconductivity/magnetic ordering behaviour is shown by ternary stannides RERhl.lSn3.6 and REOs,Sn,, respectively
(71-81). Both ErOsSn, and ErRhl 1Snj,6 for example show reentrant superconductivity
(72-81). T h e phases in the system Me-tin show at least four different structures: I, 1', 11, and I11 depending on the kind of Me (80). Phase
I compounds are cubic, space group Pm3n with a lattice constant a = 9.7
A;
I' compounds are distorted cubic; I1 are tetragonal with all = I 3.75 and C I I = 27.4A
while 111 are cubic with alII= 13.7A
(80). Phases I and I1 with Me being rare earth elements from the series lanthanum to gadolinium, and ytterbium,calcium, strontium and thorium are
superconducting between 8.7 and I .9 K. Phase I1 of the erbium compound exhibits re-entrant superconductivity (where T, = 0.97 K and
69,701.
T, = 0.57 K). Phase I1 of yttrium and scandium are superconducting at 3.2 and 4.5 K,
respectively (80).
Ternary compounds of the MnCu2Al (Heusler) type YPdZM (where M is tin, lead, indium and antimony) are superconducting. Superconducting transition temperatures are YPd2Sn 3.72 YPd2Pb 4.76 and YPdlIn 0.85 K
(82).
The phases RhPb2 and PdPb2, being Cr 6- or CuAlz-type are superconducting at 2.66 and
2.95 K, respectively (83).
T i t a n i u m . Zirconium, H a f n i u m a n d T h o r i u m
Many alloys of titanium, zirconium and hafnium with even fairly small additions of other transition elements show a big increase in the transition temperature of their hexagonal close-packed tr-phase (43, 84), see Figure 3.
Most of these effects are caused by superconducting filaments or shields of the
b-
phase or (r//l transition intermediate phases, as was at first assumed (85) and recently discussed(85). In these systems, a very careful definition of the state of the sample is necessary in order to obtain reliable results o n their
superconductivity. For example oxygen
impurities may play a role which is shown by the superconductivity of the ternary EOrtype
Table I V
S u p e r c o n d u c t i n g T r a n s i t i o n T e m p e r a t u r e s and S t r u c t u r e s of B i n a r y P h o s p h i d e s a n d Arsenides
of R h o d i u m a n d t'alladium
Corn pound
Rh,P
RhAs
Pd,P Pd,P, (h.t.) Pd,P, (l.t.1 Pd,As, Pd,As (h.t.)
Pd,As (1.t.)
Rh4P3
Rh,.,As
TCK
1.3 2.5 0.58 0.56 0.75
1
.o
0.7 0.46 1.7 0.6
-
Structure
cubic (CaF,) orthorhombic orthorhombic (MnP) hexagonal
orthorhombic (Fe,C) rhombohedra1
? ? hexagonal (Fe,P) hexagonal
b-ig ;i T r a n s i t i o n
l e ni pera I u re versus w n - c e n t r a t i o n curbes Cor
t i I a n i u ni
-
i r i d i ti nititanium-rhodium alloys,
5
after rrfcrcnce ( X i )a n rl 4.
2 4 6 8 1 0 12 14 1'6
ATOMIC PER CENT RHODIUM. I R I D I U M
phases Ti0 mRh0 2 8 7 0 0 . 1 4 and Tin.mIr0.2~700.1~
(T, = 3.37 and 5.5 K, respectively), also ZrclhlRh,).?HS00.101, Z ~ O . ~ I P ~ ~ ~ . ~ X S O I I I O S and
Z r l 1 6 S I r l l . ~ a ~ O ~ . ~ s ~ (T,= I 1.8, 2.09 and 2.30 K, respectively) (32). The A15 phases T i J r and Ti3Pt become superconducting at 5.4 and
0.58 K, respectively (32). Among the (214-type phases HfOs2 and ZrOs2 (T,= 2.69 and 3.00 K respectively) show superconductivity at higher temperatures than the C15 phases ZrIr2 and T h I r 2 (T, = 4.10 and 6.5 K, respectively) (32).
Data for the DIo2-type phases are for Th7Rh3 T,= 2.15, for Th70sj T,= 1.51 and for ThJr3 T, = 1.52 K. Th,Pt, is not superconducting above 1.02 K (32). In the system titanium- platinum, depending on sample preparation, a critical temperature between 0.4 and 4.5 K is measured. Ternary superconducting solid solu- tions based on body-centred cubic titanium-
rhodium and zirconium-rhodium have been investigated (43, 87); in all cases the critical temperature was reduced by the presence of platinum group metals.
Group
V
Elements
P h o s p h o r u s , Arsenic. A n t inion)
and Bismuth
Superconductivity d a t a for binary phosphides and arsenides of the platinum metals are listed in Table IV. It is interesting to note the difference between the critical temperature of the high and low temperature forms of Pd7P3 and PdlAs, where the high temperature form always exhibits a slightly higher critical temperature. Among the antirnonides only the B8 l-type phases PdSb and PtSb are superconducting with T , = 1.5 and
2 . 1 K, respectively (88). Among the
Fig. C l h e p r o p o d strocturr of the hexagonal trrnar) phosphicle ZrHuP. Lincs h a w been drawn to
indiratr the 1tu.t t w o -
d i ni e n s i o n a I I r i a rig u I a r clusters and also the linking
of thvse clusters through z i r c o n i u m
-
r u t h c n i u ni bonds, after reference ( 9 0 )Tabla V
Superconducting Ternary Phosphides of Ruthenium and Osmium
TiRuP 1.33 ZrRuSi 6.325 3.542
ZrRuP 12.34 - 10.56 ZrRuSi 6.459 3.778
HfRuP 12.70 - 1 1.08 ZrRuSi 6.41 4 3.753
TiOsP (1.2 ZrRuSi 6.285 3.625
1
ZrOsP 7.44- 7.1 ZrRuSi 6.460 3.842HfOsP 6.10 - 4.96 ZrRuSi 6.41 7 3.792
Compound
TiRuAs
ZrRuAs (900OC) ZrRuAs (flux) Hf RuAs ZrOsAs HfOsAs
Lattice constants
8,
Structure
(0.35 Ti FeSi 7.287 1 1.227 6.51 5
1 1.90 - 10.03 ZrRuSi 6.586 3.891
3.2 ZrRuSi 6.624 3.823
4.93 - 4.37 ZrRuSi 6.568 3.842
8.0 ZrRuSi 6.602 3.794
3.2 ZrRuSi 6.569 3.808
bismuthides, P-PdBi2 has a higher critical temperature than tr-PdBi2, T, = 4.2 and I .7 K, respectively (7, 13). A review on the superconductivity of binary compounds of the platinum metals with elements of Groups IV, V and VI has been published elsewhere (89).
Ternary hexagonal phosphides and arsenides of ruthenium and osmium constitute a new class of ternary superconductors discovered in
I 980 (90). Transition temperatures and lattice parameters of the known superconducting ternary phosphides are listed in Table V and of the corresponding arsenides in Table VI (90,91). The proposed structure of the hexagonal ternary phosphide ZrRuP is shown as Figure 4 (90).
Depending on their preparation and heat treatment, some of the superconducting phosphides and arsenides show high or low temperature modifications, which in most cases
have now been fully identified and reported (9 I ) .
No superconductivity was observed for the
LaFejPlz type compounds RERuPI2
(RE = cerium, praseodymium or neodymium). The influence of oxygen on the critical temperature of ZrRuP has been investigated (92). Oxygen is not taken into the lattice, but reduces the phosphorus concentration, which itself determines critical temperature. By specific heat measurements, the following critical temperature data were obtained: for ZrRuP T,= 1 3 , for HfRuP T,= 10.8 and for
TiRuP T, = I .2 K. T h e relatively low critical temperature of TiRuP may be caused by some kind of magnetic interaction (93).
Vanadium, Niobium and Tantalum
Solid solutions of elements of Groups V and VI in the Periodic Table, when present in ruthenium and osmium reduce their critical
Table V I
Superconducting Ternary Arsenides of Ruthenium and Osmium
I
Lattice constants
A
Compound
I
Structuret - l l -
temperatures (43). In vanadium-rich solutions the presence of I
o
atomic per cent palladium or platinum reduces the critical temperature of vanadium to below I .5 K (94).Intermetallic Phases
Since the last review article on the superconductivity of the platinum metals and their alloys practically no new binary superconductors have been found (43). Some work has been concerned with the influence of additions on the behaviour of pseudo-binary phases (7, 13, 32, 43, 100). Critical temperatures of the &phases in the systems niobium-rhodium and tantalum-rhodium have been shown to be 2.95 K for the homogeneous phase Nb0.652Rh0.348, and 424 K for the heterogeneous sample Nbo.637Rh0.363 (96). This may be caused by a very narrow homogeneity range.
The &phase in the tantalum-rhodium system is not superconducting, however (96). A I yphases with the highest transition temperatures among these compounds are Nb3Pt and MOn.7JTo.76 with T, = 9.3 and 9.05 K, respectively. Special atten- tion should be given to the peculiar A15-type phase Oso.rVo 5 which has a critical temperature of 5 . 1 5 K (7, 13, 32, 43,97).
Croup
VI
Elements
Sulphur, Selenium and Tellurium
A review of the superconductivity of sulphur, selenium and tellurium compounds
Table V I I
Superconducting Tellurides of the Platinum Metals
Compound
Pd 3Te Pd, lTe PdTe PdTe 1 02 PdTe 08 PdTe PtTe
I rTe
0 . 7 6 4.07 3.85 2.56
1 .88
1.69 0.59 1.18
Structure
hexagonal (88.1 hexagonal (88.1 hexagonal (88.1 hexagonal (B8.1 trigonal (C6.1 orthorhombic cubic (C2.1
has been presented (98). Superconductivity was discovered only among the selenides of palladium (for Pd6-7Se T, = 0.66 and for P d S e
T, = 0.42 K) and the tellurides of palladium, platinum and iridium. Data on the latter are given in Table VII.
The decrease of the critical temperature of the B8 phase PdTe with tellurium concentra- tion within its homogeneity range, is peculiar. T h e coefficient of the electronic specific heat 1’ drops from 13.5 to 9.9 callmolldegree’, while 0th the Debye temperature, is reduced from 277 to 239 K in the same range (98).
Apparently there is a sharp peak in the density of states and energy at the stoichiometric composition.
Chromium, Molybdenum a n d Tungsten
In the system ruthenium-chromium the critical temperature of the 2 0 atomic per cent
chromium alloy is 0.3 K, while at 30 atomic per cent it is higher at I .65 K (99). Both RuCr2 and RuCrl are superconducting, at 2.0 and 3.3 K,
respectively (99).
Solid solutions of molybdenum and tungsten with ruthenium show an increase in the critical temperature with increasing ruthenium content (43); the critical temperature of the &phase with 50 atomic per cent molybdenum is 10.6 K
( 100).
Further work on superconductivity in the ruthenium-molybdenum system has previously been summarised (44). The &phase RUo4Wo6niS superconducting in the range 4.67 to 5.2 K (32). Among osmium-chromium alloys the &phase
and also the Aig-phase OsCr3 are
superconductors with critical temperatures of 1.03 and 4.03 K, respectively (7, 13). The
6-
phases of osmium with molybdenum and tung- sten have critical temperatures of 5.65 and 3.8 I K, respectively ( I o I ). Superconducting iridium-chromium alloys are IrCr 3,ofP-W type, with = 0.75; IrMol with critical temperatures
Group
VII
Elements
No superconducting phases are known between the platinum group metals and Group
VII elements. Only small amounts of rhenium in iridium reduce its critical temperature, while a few atomic per cent iridium in rhenium seem to have little influence on its critical temperature ( I 02, I 03).
Group
VIII
Elements
Iron, cobalt and nickel, when present in solid solution, all considerably reduce the critical temperature of the superconducting platinum metals. T h e influence o n non-superconducting platinum and palladium is less (102, 103). Superconducting compounds are unknown.
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Sputtered Cobalt-Platinum Thin
Magnetic
Films
It has long been known that certain cobalt- platinum alloys possess useful magnetic properties which can, to some extent, be selected by choosing an appropriate alloy com- position and varying the heat treatment given. In the annealed condition these alloys can be machined or rolled and drawn to size without difficulty. As a result they are used for a num- ber of very specialised applications where worthwhile economic advantage can result from harnessing the powerful magnetic properties of these intrinsically valuable alloys.
A thin magnetic film possessing high coercivity and remanence and with high hysteresis loop squareness could find application as a high density magnetic recording medium, and in many magnetic devices. However, in contrast to bulk cobalt-platinum, the coercivity of electrodeposited cobalt-platinum films is too low to be useful for such purposes. Now Masahiro Kitada and Noboru Shimizu of the Central Research Laboratory of Hitachi Limited have reported on the development of r.f. sputtered cobalt-platinum thin films which exhibit good magnetic properties
u.
Appl.T h e films were prepared using a conventional r.f. sputtering system in which the target was either a sintered cobalt-platinum disc or a cobalt disc upon which a calculated amount of
platinum was placed, so enabling the composi- tion of the target to be changed readily.
The magnetic properties and microstructure P ~ Y s . , I 983, 54, ( 1 2), 7089-7094).
Platinum Metals Rev., 1984, 28, ( 2 ) 75
of the sputtered films, and the influence of sputtering conditions upon these were studied. High coercivity cobalt-platinum films were obtained with compositions in the range 5-35
atomic per cent platinum. A maximum coercivity of 1 8 0 0 Oe was obtained for a cobalt-20 atomic per cent platinum alloy, which had a remanence of about 9500 G.
