SCIENTIFIC ABSTRACT AGEYEV, N. V. - AGEYEV, P.Y.

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• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000100520002-1
• Release Decision: RIF
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• Document Creation Date: November 2, 2016
• Document Release Date: June 5, 2000
• Sequence Number: 2
• Publication Date: December 31, 1967
• Content Type: SCIENCEAB

' 69055
/Y. 421 ~Vr
AUTHORS: Ageyev Rogachevokayap Z. M* 3/076J60/005/03/020/048
B004/3002
All
bd
t
V
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l
4
TITLE: -
anium -
(inum
anad1
o
Stability of the P-Phase in Ti
oys
y
PERIODICAL: Zhurnal neorganioheskoy khimiis 19609 Vol 5, Nr 3, pp 619-621 (USSR)
ABSTRACT: On the basis of published data (Refs 1-4), the authors assumed
that the stabilization of the homogeneous P-phase takes place
in Ti-No-V alloys whose composition lies below the~line which
in the diagram (Fig 1) connects the binary alloy of Ti with
14% No and with 20 of V. The alloys were melted in the arc in a
He atmosphere from Ti obtained by the magne.sium-thermit process
from molybdenum powder and vanadium. The analyses of raw materials
are given In table 1, the allo 9a in table 2. Chilling took place af-
ter beating to 9000 by 70 - 10 water. The alloys were metallo-
graphically and radiographically (RKU camera) analyzed. The hard-
ness was determined by means of the Vickers apparatus. Figure 2
shows diagrams giving the stabiLity of the P-phase in alloys of dif -
ferent composition rhen heating to lo(P-6000. The highest stability
of the 21.12% of Mo and 9.72% of V alloy is at 100 0- 4000. Vanadium
additiono to about 20% have but little influence on the stability
of the P-phase, whichq however, increases with rise in the molyb-
Card 1/2 denum content. The decomposition of the P-phase of Ti-Mo-V alloys

18.4000

AUTHORS: Ageyev, N.V., Fo,-c!', A. A~, T. 1",

TITLE: Melting Chromium in a Suspenjed S.3.te

PERIODICAL: Zhurnal priklaftoy kii-imil
, Vc~ 332-337
.
(USSR)
ABSTRACT: The use of chromium as a base- flci, a1i' o-1 5
presents difficulties due to the of this metal
-)rs (A,
caused by various impurities. ozie o" ,I-!e auti-,L
Fogel, Izv. AN SSSR, OTN, E,-PE~rlmental

I I V e:-.,, ~-a pe r ar c,,;,
Technique and Methods of T t T
(ocsperimentalInaya- teldinlika _0
vysokWcikh temperaturalch) publ. 1', A %1 SSSR,
p 478) developed a method Of 1-II&J"' '1; 7 C I -I! W: 1!C
dispensed with 'lie use ol' -a ci-,i, 1,
mannev the contamlna4-lon of
gaseous impurities. The iriet~al v;3-:- a!-
Card 1/),

Meltin,z Chromium in a 3uspanded State
7 7
In purified helium atmospheve
was fed by a standard ele,~trori:*Ic, zype 1,*JPz-
60 with a frequency of' 200,000 Tne
vacuum in the melting chamber be-fc~,e ~I,e Jiitroductlon
of helium was from ',10-~ ~o
on the CDndition3 of t1he
volatilization of' the metal,
11~,- ',
undei, I . 1 - I L I d
purified by pa-sincr -it fl"Lied
with activated carbon anj Si1i,:,', I c,)C. ~-t?O J .-J
he boiling poInt of' i2quild
t
were prepared from eliec,L vaI yt I
from metal purified by ineans oV I,i~,
designated in thlo abStr!i~!t ~ao
Little sphereo (d - at)(-)ut 1b niji~:
P-ompressed from the above
L) L
melting by Slow Ic'
ir: L
Hgr The metal was ni! I I I It Lt A,j 1r T"I "1 1
Card 2/4 field until fu 1 1y molt7erL; vTjjej-jt I a .3 ,,1 'n e d

Melting Chromium in a Suspended State
Card 3/4
77636
it
SO -2- _711/52-2
2-1
off, the metal dropped into a copper casting mold.
From 100 cast samples, 25% showed a lower content
of nitrogen as compared with the initial content, 73%
showed no changes, and 2% showed a higher than initial
nitrogen content. The electrolytic chromium used in
the experiments contained: 0, 0.0084-0-013%; N, O.OOB-
0.0108%; H, about 0.001%; C, 0.020-0.025%; S, 0-003-
0.004%; Si, 0.040%; Fe, 0.030%; Al, 0.01-0-015%; Mn,
0.003%; Ni, 0.0007%; cu, omi-o.oo4%; Ti, mo6%;
Co, 0.001%. The comprezsed spheres showed 0.0103-
0.0122% oxygen on the surface, and 0.0082-0.0092% near
the center; nitrogen content was respectively 0.012%
and 0.0073%. The melting took 105 sec, and the 0 and N
content inside the cast samples was, respectively,
omo'8-o.0110%, and O.o030-o.oo6q%, i.e., the 0 and N
content did not increase duringr the melting and casting.
Similar results were obtained with the iodide chromium
(about 0.005% oxygen, and about 0.006% nitrogen inside
the cast samples). Hardness of the cast samples

Mel~ Ing Chromium in a SuspendM State
ASSOCIATION:
SUBMITTED:
77636
30v/80-33-2-11/52
(Rockwell scale B converted to Brinell) was 115-1.16 11E~,/mnj2
for the electrolyt.le, and 108-110 1,g '/mm2f'or the ludide
chvomiom. TonL311c otraln of the electrolytic chromium
castings was determined in an IM-4P type machine An
the range of 45-2100c' C. The Field point was roacheJ
above 2500 C, but even at 41 .0 C' t'h(- tlxn;~Ilu "itraln !1"j:;
onlY 3%. Compreosion tests 3howed that the Point of'
transition from plastic to brittle otate (at 150-1750 C)
wao Identical for bot1h the electrolytic and the Iodide
chromium casts. There are, f!.L-.r!J.-eq; and ~ Sjovlet vef'-
erences.
A. A. Baykov Institute of metallurgy, Academy of
Sciences USSR (Institut metailurL;ii imeni A. A.
Baykova AN SSSR)
June 6, 1959
Card 4/4

67900
0 C)
S/020/60/130/06/032/059
AUTHOR.S: Ageyev, N, V.,--.._Porresponding Member B011/B015
AS--US`SR,_ tavadze, F. W., Kartvelishvili, Yu. M.
TITLEt On the Production of Pure Chromium Chlorided'i
PERIODICALt Doklady Akademii nauk SSSR, 1960, Vol 130, Nr 6, pp 1294 - 1297
(USSR)
ABSTRACTi To obtain chromium in the highest possible degree of purity the
authors recommend the production of pure chromium chlorides
from electrolytic chromium by chloride distillation in a
chlorine current, and subsequent reduction with alkali metals
or alkaline-earth metals. In this paper they deal with the
production of pure chromium chlorides. The following reactions
are possible between metallic chromium and chlorine;
2Cr + 3C12--> 2CrC13 (1); Cr + C12 CrC12 (2); 2CrCl 3 +
+ Cr - 3CrC12 (3). The authors calculated the free energies
and equilibrium constants of these reactions from standard
data. The results (temperature dependence of the free energies
and constants) are graphically shown on figures I and 2. The
Card 1/3 thermodynamic determination shows that in the temperature range

On the Production of Pure Chromium Chlorides S/02Y60/130/06/032/059
3011 'B015
investigated reaction (1) is most likely to occur whereas re-
action (3) is most unlikely. Metallic chromium was supplied by
the Institut prikladnoy khimii i elektrokhimii AN GruzSSR
(Institute of Applied Chemistry and Electrochemistry of the
Card 2/3
Academy of Sciences of the Gruzinskaya SSR). FigurP 3 shows
the apparatus f or the production of pure drvmium d9mides.The prow-
dure may be divided into three sections: (a) degasification of
chromium; (b) chlorination of chromium; (c) purification of the
chlorides produced by sublimation. These three stages are dis-
cussed in detail. Degasification at 400-450 0 in a vacuum of
10,4mm during 1,0-1-5 h was sufficient to eliSnate the entire
hydrogen. Chlorination is effective at 595-605 . The chlorina-
tion time is to a considerable extent determined by the rate
of chlorine addition and the amount of weighed chromium portion,
Chlorination -took about 50 minutes at a chromium quantity of
20-30 g. At a slow chlorine passage CrCl 2 is produced. It is
necessary to purify the rihromium chlorides under the exclusion
of air and steam in vacuum or in pure chlorine because the
chromium trichloride vgpors oxidize easily in the air. CrCl
dissociates above 1300 , signs of dissociation aref however"

86392
S/020/60/135/002/016/036
19.-7 SW B016/BO52
AUTHORS: Agey_~N~~orresponding Member of the AS USSR and
Shekhtman, V. Sh.
TITLE: The Nature of Sigma Phases
PERIODICAL: Doklady Akademii nauk SSSR, 1960, Vol. 135, No. 2,
pp. 309-311
TEXT: The authors investigated the order of sigma phases in the systems
Cr-Re, Mn-Re, and Re-Fe. They studied annealed binary alloys with 37 at%
Cr (the sample was obtained from Professor Ye. M. Savitskiy's laboratory) ,
47.7 at% Mn, and 55 at% Fe. According to microstructural and X-ray
analyses, these alloys belong to the single-phase regions of a-phases in
the state diagram. Accordingly, formulas were chosen for the calculation
of structural amplitudes which, on the basis of crystallochemical data,
are ascribed to these compounds with all reservations: Re 18 Cr 12 , Re 16mn,4,
Re 12 Fe 18' Table 1 shows the variants of ordered atomic distribution in the
Card 1/5

66392
The Nature of Sigma Phases S/020/60/135/002/016/036
B016/BO52
compounds concerned. These variants follow the symmetry of space group
P42/mnm to which the structure of a-phases belongs. The authors'
calculations showed that in most cases a distinction between statistical
and ordered distributions of atoms is possible on the basis of the
interrelations of chosen lines. However, in the case of the Re-Fe alloy, V~
it was also necessary to study lines (311) and (002). Their intensities
were determined by a YPC-500 (URS-50I) diffractometer with an MCTP-4
(MSTR-4) counter. The curves were recorded by an 3nn -09 (EPP-09)
potentiometer. A comparison between experiment and calculation shows that
the above-mentioned alloys are ordered. The atomic distribution in the
cells of a-phases is correlated to 'a coordination number and depends on
the position of the components in the periodic system. The diagram of
Pig. 1 shows the average concentration of Re in the a-phases of V-Re,
Or-R, Mn-Re, and Fe-Re (Refs. 13-15) as a function of the group number
of..the second component. It was thus found that the Re content decreases
with increasing group numbers. Their explanation of this phenomenon is in
accordance with the opinion of other researchers; they arrive at the
conclusion that in the four last-mentioned systems, rhenium has an
Card 2/5

-86392
The Nature of Sigma Phases S10201601135,10021016lo36
B016/BO52
electron excess as compared to the hypothetical level. The hiCher the
valency of the second component, the'smaller ti
he Re amount necessary for
an electron concentration character"i-stic of a-pha' ,ses. It is assumed that
the formation of a-phases in the 'systems Re,Mn and Re-Fe can be. explained
by a higher metal valency of Re as compared to the elements of the first
transition group, although these a-phases do not follom, the well-known
rule according to which the element-s forming c-phases lie on both sides
cf the dividing line between the sub-groups VI A and VII A. There are
1 figure, 2'tables, and 15 references: 6 Soviet, 4 US, 4 British, and
1 Polish.
ASSOCIATION: Institut metallurgii'i~. A. A. Baykova Akadem-1i nauk SSSR
(Institute of, Illetallurgj immeni A. A. Bayko-v of the Academy
of Sciences USSR)
-SUBMITTED: August 3, 1960
Card.3/5
...... ... ... .

86392
The Nature of Sigma Phases 3/020/60/135/002/'016/036
B,016/BO52
Text to.Fig. 1:.Re content of the 6-phase
as a function of the grQup-number of the "I
Second period.
V Y) vll Y111
1-310
Card 4/5
- - - - - ---- ___-_... __ - -.;, .. - . ~ -1 ~'_ -', - ~ ~ - -_ _ __ ~-"-I-'- - - "' 7'

66392
~10201601135100210161036
B016/BO52
CBRUHHOrl Rf"cril
riepnqAjiqe-
e3y.IbTaTbl, 3 A 1 2 1 2 13- 1 A
Ai 135-'q
aflai)jHem, 2 hi 1 .1
B )Re 2 Re 2Cr n 2 Mn 2 hin 2 Re 2 JMn 1. Mn Fe 1. Fe 2 Fc 2 Rd
iR: 4Cr iRe 4Mn 4 Re I Mn :1 Mn 4 Re 4 Re 4Fe ; F6 I Re 4 Ft
10 fol'y
R 4 Re 6 Re 8 Re 8 Re Re G Re 4 Re 6 Re 8 Fe 8 Fe k Re 6 Re
lipeAc'T8B- 4Cr 2 4 hIn 2 Ain A Mn 2 hin I Fe 2 Fe
8Fe 8 Re 8 Fe 8 Re
JX hieTaj. Cr 8Re .8 8 Mn 8 Re 9 Re 4 Re 6 Mn
4Ain I I
Re 4Re SRe aRe 4 Rell Re 8 Mn i Re 0 Re 6 Re A Re I Re 8 Fe
Re, Cr 4 cr 4cr 4 %In Mol 4Mn,2 hin 14 Fe 4 Fe
lext t o' Tabl e 1: 1 Position; 2 c;oordination number.
LT.
Card 5/5

ALISOVA, S.P.;KOLESNIKOVA, T.P.; MARKOVICH, K.P.; PETROVA, L.A.; ROGACHEV-
SKAYA, Z.M.; AU7EV, N. ., red.; NOSUDA, R.Ya., red.; MUKU, S.Ya.,
tekhn. red.
[Conatitution4l diagrams of metal systems published in 1958) Diagrammy
sostoianiia metallicheskikh sistem, opublikovannye V 1958 otu, Pod
red. N.V.Ageyeva. Moskva, No-4- 1961. 402 p. ~1111 14:12)
(Phase rule and equilibrium)

S/180/61/000/005/013/ol8
E193/E383
AUTHORS: Ageyev, N.V-., Karpinskiy, O.G. and Petrova, L.A.
scowI
TITLE: Stability of the beta-solid solution in titanium-
iron-chromium alloys
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Otdeleniye
teldinicheskikh nauk. Metallurgiya i toplivo, no. 5,
1961, 86 - 89 + 1 plate
TEXT: The object of the present investigation was to study
the effect of a third alloying element (iron or chromixun) on
the stability of the P-phase in binary Ti-Gr or Ti-Fe alloys.
The composition of the experimental alloys is &iven in a table.
Hardness measurements, metallographic examination and X-ray
diffraction were used to study the phase transformations in
specimens prepared from alloys which had been iiiielted in an
argon-arc furnace, hot-forged, scalped and homogenized by two-
hours treatment at 900 OC. In the first series of ex 9eriments
the constitution of alloys quenched from 800 and 900 C was
studied. The results are reproduced in Fig. 1, showing the
Card 1/0 q

S/180/61/000/005/013/018
Stability of .... E193/E383
Ti-rich cornar of the metastable constitution diagram of
Ti-Ve-Cr alloys at 900 0C (broken line) and 800 OC (continuous
line); the regions above and below these lines comprise alloys
consisting, respectively, of p+w and P-phase only. These
results are in agreement with the earlier findings of Ageyev
and Petrova (Ref. 5 - DAN 555R, 1961, v. 138, no- 2, 359-360),
according to which alloys with an electron concentration >,4.2
consist of a single P-phase, whereas those with and electron
concentration < 4.2 have a two-phase (P+w) structure. In the
second series of experiments, the stability of the metastable
P-phase, obtained in alloys 2, 4, 5 and 7 by quenching from
900 0C, was studied on specimens aged at loo - 4oo 0C for
periods ranging from 15 min to 100 hours. The results are
reproduced in Fig. 2, where the constitution of an alloy
containing 4.090" Fe and 6.201,1.,!, Cr is plotted as a function of
temperature (t, OC, vertical axis) and time (-C, min,
horizontal axis); the continuous lines divide the diagram
into three regions: P-phase regions (circles); (p+w) region
(crosses) and ((x+0) region (squares)~ The numbers ascribed to
Card 2,V I/

s/18o/61/000/005/013/ol8
Stability of .... E193/E383
experimental points denote the hardness (1cg/mm2) of the
corresponding specimens and the broken lines represent the
boundary of the maximum-hardness region. It will be seen
that alloys with the (P+w) structure are relatively hard, the
hardness increasing with temperature of the ageing treatment.
This effect is associated with the degree of dispersion and
the quantity of precipitated u-phase. Laue photographs of the
ti-Fe-Cr alloys, aged at 300 - 400 OC, showed additional
reflections (satellite spots) situated near those produced
by the matrix lattice. This effect was attributed to a change
in the periodicity of the lattice in sub-i-Acroscopic crystal
regions caused by localized variation of the concentration
of supersaturated solid solution during the formation of two-
dimensional nuclei of the new phase, whose composition
approached that of the precipitated phase in equilibrium with
the matrix. The dimension of the Ti-enriched regions were
calculated from the angular displacei-,iont of the satellite spots
and it was found that they depended on the composition of the
alloy and the ageing time and temperature, being approximately
Card 3/f ZI

5/180/61/000/005/013/018
Stability of E193/E383
a
150 A in the 3.19 wt."' Fe and,5.99 wt.%D Cr alloy, aged for 15 min
at 400 OC, approximat'ely 125 A in simila 1y treated 11.09 wt.0c",
Fe and 6.20 wt.0' Cr alloy and about 100 k in the 4.15 wt.%' Fe
6.33 wt.96' Cr all"oy. The effect of temperatureuas more
pronounced: in the case of the 4.09 wt.0,L. Fe - 6.2 wt.clp Cr alloy,
it t ok 15 in for the size of the Ti-enriched zones to reach
125 1, whenmaged at 400 0C, and 81 hours when aged at 300 0C.
The change in the particle size and quantity of the precipitated
w-phasew~s accompanied by enrichment of the P-matrix, whose
composition tendbd to approach that of the eutectoid. This
tendency was indicated by the variation of the lattice parameter
of the P-phase which, in the 4,,0 Fe -- 3i,64 ivrt.' Cr alloy,
changed from 3.250 kX after quenching,to 3.182 kX after 7 hours
ageing at 400 0 C. The results of the present investigation
showed that the decomposition of the supersaturated solution
in Ti-rich Ti-Fe-Cr alloys took place in the following manner:
P->B +(W(P ) + P P + W, P +
iIIII)OV. enrichj--~ enrich. enrich.
+ a -*> a + chem. compound.
Card 11/0 ~/

Mao
331LO
s/18o/61/ooo/oo6/oi4/O2O
E193/E383
AUTHORS, Ageyev, N.V., Karpins1dy, O.G~ and Petrova, L.A.(Moscow)
TITLE: Stability of the beta-solid solutio-i iii titaniuta-
iron-vanadium. alloys
PERIODICAL-, Akademiya nauk SSSR. Izvestiya, Otdeleniye
teklinictieskikh nauk, Metallurgiya i toplivo,
no. 6, 1961, 10-7 - 129 + 1 plate
TEXT,, The object of the present investigation was to study
the effect of a third component (V or Fe) on the stability of
the a-phase in binary Ti-Fe or Ti-V alloys, The composition of
the experimental alloys is given in a table.. The alloys, remelted
several times in an argon-arc furnace, were hot-forged at
900 - 950 0C into rods measuring 9 x 9 x 100 izim. After machining-
off the oxide shin, the rods were hoi,.iogenized by a five-hour
vacuu-m treatment at 900 0C, followed by furnace-cooling, The
pbas e-transf ormat ions were studied by X-ray diffraction and
hardness measurements. The results of examination of snecifilens
quenched from 900 and 800 0C are given in Fig. 1, in the form
of a metastable constitution diagram (the Ti, V and Fe contents
Card 10

33180
s/18o/61/oOo/OOG/ol4/o0.o
Stability of the E193/E383
-ire given in alloys situated above the broken
C or
continuous lines represent those in which the P-phase can be
retained on quenching from 800 or 900 0C, respectively; decom-
position of the P-pliage in alloys situated beliow these lines
cannot be prevented by quenching, and the alloys in this
composition range consist of P- and w-phases- In the next
series of experiments the alloys 7-. Q8, 9 and 10, solution-
treated at 900 aC, were aged at various temperatures for various
times,. Typical results are reproduced in Fig. -2, showing the
constitution of the Ti-3.74 Re - 14.68 V (graph a) and
Ti - 3.87 Fe - 16.68 v (graph 6) alloys as a function of ageing
temperature (vertical axis, 0C) and time (horizontal axis., iiiiii).
The continuous curves divide each diagram iiito the P, P+w and
a+P regions; the numbers, ascribed to the experimental points,
denote the Vickers hardness number of the alloy, while the broken
lines forin boundaries of the inaximum-hardness regions. In
general, it was found that with increasing alloyin8-additions
content; the precipitation of the w-phase in solution-treated
Card 21e

Stability of the ....
33180
s/1UOo/61/ooo/oo6/ol4/020
E195/E383
Ti-Fo-V alloys aged at 1*00 OC was suppressed, the (P + w)
ranc,c became narrower, the quantity and particle-size of the
w-phase decreased and the hardness of the alloy was reduced to
an extent which increased with increasing V content. It would
appear that in alloys with 23 - 25' V and 3 - 4',,'. Fe, aged at
4oo OC, the (a + P) structure is formed directly from the
P-solid solution without passing through the interi,,iediate
(P + w) stage. The presence of additional (satellite) 0
C
reflections on Laue photographs of specimens aged at 400
was taken to indicate the formation (in the initial stage of
the process) of two-dimensional nuclei of the w-phase surrounded
by Ti-enriched P-solid solution. The size of these nuclei,
calculated from the angular displacement of the satellite
reflections, was - 220 X . The satellite reflections disappeared
on further ageing and the Laue photographs showed the lines of
co-phase and Ti-enriched P-solid solution only. It was concluded
that decomposition of the P---olid solution in Ti-Fe-V alloys
took place in the following manneri
Card 3/0 1

33180
S/180/61/000/006/014/020
Stability of tho .... E193/E.383
) + 0 ' --'~ 0C.'nrich. + Penrich. +
iIIII)OV 011rich-i
+ a _> a + clicinical compound.
There are 3 figures, I table and 4 Soviet-bloc references.
SUBMITTED, March 3, 1961
Fig. 1:
V.6ec.y.
is Iz 8 'Fe
D
Z20
x
x TL
V
76 80 84 88 .92 96
Card Tt. 6e% /0 w t

88475
S/078/61/006/001/018/019
B017/BO54
AUTHORSt Ageyev N. V., Karpinskiy, 0. G., Petrova, L. A.
TITLEt Mechanism of Decomposition of Solid P-Solution of
Titanium - Rhenium Alloys
PERIODICAL: Zhurnal neorganiaheskoy khimii, 1961, Vol. 6, No. 1,
pp. 251 - 252
TEXT: The authors studied the mechanism of decomposition of solid
P-solution of titanium - rhenium alloys by metallographic and X-ray
analyses, as well as by Vickers hardness measurements. The alloys were
produced at the Laboratoriya redkikh i blagorodnykh metallov i splavov
Instituta metallurgii Akademii nauk SSSR (Laboratory of Rare Metals,
Precious Metals and Alloys of the Academy of Sciences USSR). A figure
schematically shows hardness and structure of a titanium alloy with
19.91 % by weight of rhenium, which was hardened at 900 0C. The solid
P-solution of the titanium alloy with 19.91 % by weight of rhenium is
decomposed on heating at 4000C with separation of theci-phase; with
extension in the reaotion time, the &j-phase passes over into the a-phase.
Cara 1/2

88475
Mechanism of Decomposition of Solid P-Solution 5/078/61/006/001/018/019
of Titanium - Rhenium Alloys B017/B054
The mechanism of decomposition of
alloys proceeds according to the
hardness of 13-alloys of titanium
distortion of the crystal lattice
1 figure and 5 Soviet references.
solid P-solution of titanium -
scheme P --+A + ci --+ /3 + a. The
with rhenium is explained by a
of the solid P-solution. There
rhenium
increased
are
SUBMITTED: August 2, 1960
Card 2/2

255318
AUTHORS: Ageyev, N. V.,Karpinskiy,
TITLE: Stability of the A-phase
alloy
S/078/61/006/008/018/018
B127/B226
0. G., Petrova, L. A.
solution of a titanium-chromium
FERIODICALt Zhurnal neorganicheskoy khimiit v. 6, no. 8, 1961t 1976-1978
I -
TEM This is to continue a series of studies on the &-phase Ti-Cr alloy,
and to clarify the balancing of the metastable phase and the mechanism of
dissociation at 100 - 4000C. Titanium and chromium iodides were used as
initial materials which contained 1~6 of carbon and, as gaseous additions,
0.01% of oxygen and nitrogen, and OoOO1% of hydrogen. The iron and
silicon content did not exceed 0.05%. The components were fused in an
arc furnace with tungsten electrodes and an argon atmosphere. The alloy
was kept in molten state at 900 - 9500C with intermediate heating for
5 - 15 min. The melt was tempered in a muffle furnace at 9000C for 2 hr,
and then gradually cooled in the furnace. Heat treatment of th I samples
was carried out in quartz ampuls evacuated to a pressure of 10- mm Hg.
The samples were metallographioally and roentgenographically examined;
hardness was determined by the Vickers method and under a pressure of 10 kg.
Card 1/4

C
Ii/078/61/006/008/018/018
Stability of the ... 25518 B127/B226
The A-phase can be obtained in metastable state in melts of 9% by weight
(6-.4 at%) of Or by tempering at 800 and 9000C. All other alloys con-
taining less than 9016 of Or showed )~- and u)-phase structures. For this
Ftabilization, different values are given in publications. They are ex-
plained by the impurity of the substances used and by the different rates
of tempering of the alloys. In the present case, the stability of the
0-phase of alloys havi-ag 9.14 and 9.790% by weight of Or was studied at
temperatures'of 100 - 4000C. The stability of the A-phase is graphically
shown in Figo 2, The solid lines comprise the structural range; the dotted
onea show the range of maximum hardness, the values of ich are given in
figures. The P-phase dissociates as followsi A---#A+ tca~(~reduced)
+ oconcentrated3---#4Aooncentrated +W _-pAconcentrated + a joL + chemical
compound. There are 2 figures, 1 table, and 12 referencesi 10 Soviet-
bloc and 2 non-Soviet-bloo. The two references to English-language
publications read as followss Ref- 71 Fo B, Cuff, N. J. Grantp C. F, Floe.
Trans Amer# Inst. min. (metall). Engre, 194, 848 (1952); Ref. 8:
D. J. Me Pherson, M. G. Fontana. Trans Amer. Soc. Metals, _43, 1098 (1951).
SUBMITTED: March 6, 1961
Card 2/4

2383o
10 L( j-1 NrL, S10201611138100210191024
B103//B220
AUTHORS: Ageytv, N. V., Corresponding Member AS USSR, and
.-P. et rova, L, A.
TITLE: General rules for the stabilizing of solid beta solution
in titanium alloys
PERIODICAL: Akademiya nauk SSSR. Doklady, v. 138, no. 2, 1961, 359-360
TEXT: The authors deecribe the factors influencing the minimum critical
content of alloying addition needed for stabilizing the beta phase in
titanium alloys. These factors have to be aso 'ertained in order to
e3tablish the -eneral rules of the above stabilization. Tabld 1 shows
these minimum concentrations for 11 stabilizers by which a monophasa
structure of the solid beta solution in metastable state is obtained at
room temperature. The sequence of these elements corresponds to their
activity as stabilizers. Of these factors, the position of the element
in the Periodic System is of particular importance. The authors state
that the activity of the elements increases with their distance from
titanium in the System. This dependence is due to the influenoe exerted
Card 1/5

23836
S/020/61/13B/002/019/024
General rules for the stabilizing of... B103/B220
by the dissolving component of the solid solution on the rearrangement
of the lattice of the titanium solvent on quenching,. This rearrangement
is made difficult in 7,he beta phase *Dy introduction of a foreign atom,
i.e. the more difficult, the greater is the chemical difference between
the atoms of titanium and those of the other component of the solid solu-
tion and the stronger these atoms differ in size. The chemical nature of
an atom as well as its size depend on the number of electrons in the atom,
i.e, on the electron concentration. Thus, one is able to clarify the
interdependenoe between the oritioal. stabilizing concentration of the
beta phase on quenching and the electron concentration. Table 1 shows
thia concentration, the number of electrons being considered to correspond
to the group number of the relevant element. From this fact the authors
oonclude that the metastable beta phase can be obtained in titanium
alloys at a practically equal number of electrons (averaging 4.2 per atom).
These rules were oheoked by the authors for tertiary alloys: Ti - Fe - V
(Fig. I ), Ti - Fe - Cr, Ti - V - Mo, and Ti - Mo - Mn. If the electron
concentration is known at which the beta phase is obtainable, one is able
to calculate the compositions of the alloys which will give the structure
of the solid beta solution on quenching. Fig. 1 shows the ternary
Card 2/5

S1020J611138100210191024
General rules for the stabilizing of... B103/B220
metastable diagram of the phase composition in the system Ti -Pe -V. The
straight line drarn in the corner of titanium, which separates the range
of the beta phase from that of the P+w-phases has been obtained by
connecting the points oorre'sponding to the critical stabilizing concentra-
ti%jns of the alloying elements in the binary system Ti -Fe and Ti -V.
Ternary alloys having an electron concentration below 4.2 are in the range
of the P+o)-phases, A titanium alloy with 3.11 atom% Fe and 5.37 atomYo V
(electron concentration 4.18 el/at (1)) has been Droved to be such an
alloy. The following alloys, however, have the structure of the beta
phase: 4.35 atomep of Fe and 7.64 atom% of V (2), 2.61 atoeo of Fe and
11 .4 atom~o of V (3) as well as that having 2.86 atom5 of Pe and 14.18 atom%
of V (4) whose electron concentration amounts to 4.24, 4.21, and 4.25 eVat,
respectively. The above rule was also confirmed for further ternary
alloys. There are 1 figure, 1 table, and 6 references: 5 Soviet-bloc. and
1 non-Soviet-bloc.
ASSOCIATION: Institut metallurgii im. A. A. Baylova Akademii nauk SSSR
(Institute of Metallurgy imeni A. A. Baykov of the Academy
of Sciences USSR)
Card 3/5

ROGACHEVSKAYA, Z.M.;.&QEMV,-NV,, red.; 140SKVINA, R.Ya., red.;
SVYLINA, S.I., tekhn. red.
[Constitutional diagrams of metal systems, published in 1960
(no.6))DIagrammy sostoianiia metallicheskikh sistem, opubli-
kovannye v,1960 godu (v3-pusk 6) [By] Z.M.Rogachevskaia. Pod
red. N.V.Ageeva. Moskva, Proizvodstvenno-izdatellskii kombinat
VINITI, 1962. 173 p. (MIRA 16:2)
(Phase rule and equilibriwn) (Metallography)

GOLIJIVIN, Turiy Mikhaylovich; AGEYEV, N.V. p otv. red.; DRAGUIiOV, B.S. p
red.; RAGRAMOVA, I.A., tekhn. red.
[Heats of formation and types
crystals] Toploty obrazovaniia
neorganicheskikh kristallakh.
1962. 94 p.
of chemical bonds in inorganic
i tipy khirdcheskoi sviazi v
Moskva, lzd-vo Akad. nauk =RY
- (MIRA 15:5)
1. Chlen-korrespondent Alcademii nauk SSSR (for Ageyev).
(Crystals) (Heat of formation) (Chemical bonds)

VOL, Abram Yevgenlyevich; AGEYEV,, N.V red ; AIRIKOSOV, N.Kh., doktor
khImenauk, red&j--KGMWV, I.Iop doktor khim,nauk, red,;
SAVITSKIY.. Ye.M.,, doktor IdLim.nauk, red.; OSIPOV, K.A., doktor
tekhn.nauky red.; GUSEVA, L.Nsy kand,khim,nauk; red. ;
MIRULOVSKAYA.. M.S., kand.khim.nauk, red.; SHKLOVSIWA, I.Yu.,
red*; MURASHOVA, N.Ya., telchn.red.
[Structure and properties of binary metallic systomB] Stroenie
i svoistva dvoirqkh metallicheskikh sistem. Pod rukovodstvom N.V.
Ageeva. Moskva, Fimatgiz. Vol.2. (Systems of vanadium, bismuth,
Irldrogen, tungsten, gadolinium, gallium, hafnium, germanium, holmium,
dysprosium., europium, iron] Sisteny vanadiia, vismuta, vodoroda,
vollframa, gadoliniia, galliia, gafniia, germaniia.. gollmiia, dispro-
ziia, evropiia, zheleza. 1962. 982 p. (IMIA 15:5)
1. Chlen-korrespondent AN SSM (for Ageyev).
(Alloys) kSystems (Chemistry)) (Phase rule and equilibrium)

S/59
62/000/007/002/040
D267% 307
AUThORS: Ageyev, N.'V. and Petrova, L. A.
I------------
HTLE: Stability of the B-solid solution in titanium alloys
SOURCE: Akademiya nauk SSSR. Institut metallurgii, Titan i yego
splavy. no. 7, Moscow, 1962. Metallokhimiya i novyyp
splavy, 26-34
.,TEXT: Earlier papers include metastable phase dk4grams of titani-
um alloys with Fe, Mn, Ni, Mo, Cr, W. V and Nb, and data of the
critical contents of alloying elements required to obtain a single-
phase structure of B-solid solutions. These phase diagrams belong
to one of the main types: (1) Alloys quenched from the B-phase re-
gion have the structure of metastable phases d,', w and 13; (2) in
addition to these phases, also the o~" phase is present. Whereas
the phases c(I and o~" Lnay exist in alloys either separately or in
the presence of other phases, the w phase always coexiate with the
c/,-phase, and is characterized by a high degree of dispersion. The
critical content referred to above is the smaller, the farther the
Card 1/2

Stability of the ...
S/59 YD 62/000/007/002'/040;
D267 307
position (in the Periodic Table) of the alloying element is from
that of Ti; in terms of electron concentration the critical con-
tent is always 4.2 e.lectrons/atom. Thus in the system Ti-Fe-V an
alloy with the electron concentration of 4.18 was in the region of
P + to phases, whereas alloys with electron concentrations 4.24,
4.21 and 4.25 had the B-jhase structure. The survey includes also
the results of research of the stability of metastable solid solu-
tion 3 and of the mechanism of its decomposition at various tem-
peratures up to 50000; up to the 'room' temperature this solid so-'
lution did not decompose (with only one exception). At higher tem-
perature the stability is in general the higher, the greater the
content of the alloying component. There are 11 figures and 1
table.
Card 2/2

AGEYEVI N.V. (Moskva); KARPINSKIY, O.G. (Moskva); PETROVA, L.A. (Moskva)
Reply to IU.A.Bagariatskii's and G.I.Nosova's letter. Izv.AN
SSSR. Otd.tekh.nauk. I*t.i topl. no.4:188 JI-Ag 162.
(MIRA 15:8)
(Titanium alloys-Metallography) (Bagariatskii, IU.A.)
(Nosova, G.I.)

AGEYEV, N.V.; GOLUTVIN, Yu.M.
. . 1. ~ ~7
M.Lomonesov and cristallochemistry. Vop.ist,est.i tekh.
no,12:62-66 162. (YjRA lrl,:4)
(Lomonosov, Mikhail Vasillevich, 1711-1765)
(Crystallography)

Y11
AUTHORS:
S/02()/62/143/004/024/027
B101/B138
AR 'gyev, N. V". Corresponding Member AS USSR, and Shekhtmanj
V. She
TITLE: Ordering of a solid solution on a-Mn base
PERIODICAL: Akademiya nauk SSSR. Doklady, v. 143, no- 41 1962, 922-924
TEXT: The ordering of the single-phase alloy confaining 20% by weight
(6.9 at. %) rhenium and 80% manganese, which almost corresponds to the
maximum solubility of Re in a-1,111n, was investigated by Debye patterns.
The following atom distributions were examined:
Distribution of the atoms Legend: P - position;
P 'C ~ IA S I I Il III
2 a 1 2.74": 2Re 2Mn C - coordination number;
8 0 i162 75' Re+614n, Re+6)Lrn 4Re+4Mn IA - mean interatomic
24 9~ 11 3E 64 4Re+54Mn 201n. 2411n 2421 distance, X; S - statisti-
2AIRI )-12'2.571 ~ 2411n ~ 2411n Win cal distribution.
The calculation of structural amplitudes for R Re " 1-37 and Run - 1.30,
Card 1/3

5/020/62/143/004/024/027
Ordering of a solid solution... BJOI/B138
based on equations availablb for the I-43M space group, showed that the
orderin of the alloy could be evaluated by the intensities of the lines
(321), &00), (411, 330), (332), (422), (431, 510). Samples produced in
an HF furnace and annealed at 750, 600, and 950 0C, were examined in the
cast state, together with electrolytic Mn for a reference. Results: (1)
Tholine intensity in the a-Mn Debye pattern agrees well with calculations
for the case of disordered distribution. (2) The line intensities do not
differ for cast and annealed samples. Heat treatment, therefore, does not
modify the atom distribution. Re atoms in the solid solution are
partially in positions (a) and a , without preferred occupation of either-t
i. e.,- there is a tendency toward ordered distribution corresponding to
variant I. This is indicated by the intensifying of line (321)' until it
is almost as intense as (400), and by the approximately equal intensity of
lines (422) and(431, 510), while line (332) fades slightly. (4) Only part
of the Re atoms occupy positions corresponding to the maximum goordination
cumber. About 2 Re atoms each settle in positions (a) and (a). The
tendency- of the larger Re atoms to occupy positions corresponding to the
largest interatomic distances confirms the relationship between the for-
mation of phases with a-Mn structure and the scale factor. There are I
Card 2/3

8/02 62/143/004/024/027 q
Ordering of a solid solution... B I 01YB 138 i
r
figure and 2 tables.
SUBMITTED: November 29, 1961
~ I
Card 3/3

912
S/OA6~62/143/005/010/018
B145/B138
AUTHORS: Ageyev, N. V. Corresponding Member AS USSR, and Shekhtman,V.Sh.
TITLE: A new compound in the system rhenium - iron
PERIODICAL: Akademiya nauk SSSR. Doklady, v. 143, no- 5, 1962, 1091-1093
TLXT: Re - Fe alloys with 40, 50 and 60~ by weight of Re were investi-
gated metallographically and by X-ray diffraction analysis. Carbonyl iron
and carbonyl rhenium (99.%4) were used as starting materials. The samples
were annealed at 750, 800, 950, and 10500C and quenched from 1200 and
13000C. Powder patterns were taken in CoK.,radiation without filter, in an
PKA(RKD) camera. The patterns from specimens quenched from 1200 and
13000C or annealed at 10500C showed t,wo systems of lines corresponding to
the solid solution rFe - a phase. At lower annealing temperatures, the 6
phase lines disappeared, and, besides lines of the a ~750 and 80000- and
- (95000 solid solution, reflections of a new phase ~rl phase) appeared.
I
ccording to the X-ray pattern the alloy with 60~ Re is very close to the
single-phase region of the new compound. The lines of the I phase fit
in on the assumption of a cubic body-cen'lered lattice. 8.9t~ kX was ob-
Card 1/2

S/020/62/143/005/010/018
A new compound in the ... B145/B138
tained for the a parameter of the unit cell (platinum standard). From
this, z, the number of a-Loma per unit cell is calculated as 58-1, using
density (12.92 g/cm3). The X-ray pattern of the fl phase is very similar
to that of a-manganese (z - 58). Differences in intensity are due to the
ordered distribution of Re and Fe in the hase. Proceeding from the
distribution 2(a)z 2 Re, 8(c): 8 Re, 24 8 Re, 16 Pe, 24(gf): 24 Fe,
the line intensities of the ft phase were calculated by means of the
equation IjLpIF1 2 (L - I + oos229/sin 220 0 cosQ, p - repetition factor,
JFJ - modulus of the structure amplitude), and agreed well with the
measurements. This means that the new compound has a structure of the
a-manganese type with ordered distribution..of the atoms in the unit cell.
Compounds of the same structural type might exist in all systems with
metals of the IVA, VA and VIA subgroup (except Cr and V). There are
I figure and 2 tables.
ASSOCIATIONt Institut metallurgii im. A. As Baykova (Institute of
Metallurgy imeni A. A. Baykov)
SUBMITTEDs November 29, 1961
Card 2/2

3/020J62/146/oO2/007/013
B101/B144
AUTHOR3: Ageyev, N. V., Corresponding Member AS USSR, G.rankova, L.
TITLE: Effect of aluminum on the stabili7ty of the 5-phase in
titanium - molybdenum - iron alloyp
PERIODICAL: Akademiya nauk SSSR. Doklady, v. 146, no. 2, 1962, 351-354
TEXT: Titanium alloys containing 6-7-13-5` Mo, 2.2-1M, Fe, and 1-3;', Al
were studied radiographically and metallographically and their hardness
was determined in order to explaia-differences in the published data.
Results: (1) All alloys except those contain'ing 6-7','6' Mlo, 2.21,4 Fe, and
1-liof Al form single-phase solid P-solutions when hardened at 7000C. -
Alloys containing 6-7~ Mop 2.21,of Fe, and 1-21,'j' Al form the P-phase after
hardening at 9000C, those containing 3~ Al form it after hardening at
10000C. (2) In alloys containing 6.7' Mo, 2.2~/fa Fe, 1-3L Al, the P-'phase
decomposed within 15 min at 2000C. Between 200 and 3000C, the (-)-phase
was formed and remained stable for 100 hra. The hardness increased with
the ageing temperature. At 4000C, a P+W--+ P+a transition took place in
Card 113

ACCESSION M AT4046210 S/0000/63/000100010005/0009
1-Hos: 610-4- _rOv
1AUTHOM UM, ASO a
L, A. (Moscov)
TITLE: Stability of B-solid solutlox~ in ti-tanium-n-iobium and tita--
nium-tun sten alloys
11
SOURCEt Yubileynaya konfe -rentsiva po fiztko-kh1michesko -mu - a-na- lizu.
Nevosibli sk, 196,3... Pi Zi c-i-CYleyri Cal in 31-
tr U r d.
vsq_.q'~: YA konfeients- AN SSSR,
IQ63, 5-')
T0 P I C T A,, S t I t a n i u m Lase a ~-3- all~v , t i t an i urn
tungsten alloy, beta tiLaniurr. a I a a j T1. s r a D I lity, beta
titanium stabilizer
ABSTRAM The effect of niobium or tunRsten on the stability of the
3-phase and tne mechanism of its in titanium-base
alloys were studie4,-. In titan!uu.-n,,(,t.,_im iii c~, ~ with 36.8Z Nb, a
metastable 8-phas -e can be preserved !: V ',,Ue11L*1 I -Ig 4L rOM 80LJC . I n a
I o y a w i t h 34 . 6-36 . 5 0% Nb , quenched r~;r L-,e 5ame emperature , the

ACCESSIOU NR: AT4046210
8-phase was found to be partially decomposed. X-ray diffraction
patterns of tnese alloys showed, in addition cc th-e lines of B-phaae,
those of tne 3--phase, whose suant:tv ~ecreasc in t~ie
niobium content and in the annealfrip tem-erature, It was found, how-
ever, that even in these allovg the :--rhase can te -,reserved bY art
increase in the cooling r a t e . No L.--h&se w a s fourid. In titanium-
tungsten al loys wi th 26 . b4Z W, the w a ~ ~,reserved by quench~.ng
from S00C. Allovs with I t, , -, " - " I ~ -.1 . I e I ~ I . _1 , have an
Q-Phase s tructure, and, a c v 9 a 4- - -s t r u c t u r e
In the al lov .7ith 3 4s 4 N t~
~-nhase begin! to
o e c o mp o a e a f Le r
. n e p r i m-, r v
product of decomposition is w-h~ssc)which ther. c~i'qnqes to a-phase, In
the alloys wi,.h 26. 64Z or 2in. ~-e -i u 0 t~ , t tie B-vhai e
begins to decompose after i hr at 3 A v u k- t h e 8-phase dt -
composes immediately, with -,, r v ' -- 1. -, E; 4 - - a F, e A 11 t h o u g It I t
was not possib 1e precisplv to comnare h e s I a', t ' v o f S-Phase of T t-'U
11 - N' i , t h e r e s s ~ m v r c -3 1a
with that of e that tungsten a
stronger atab4 ' 11.zer of the r~g, art, has: 4
figures and 2 tables.
Card 2/ 3

0
SUB CODEi MM
ATD PRESS., 3129
Card V3

AGEM. N. V., and
"On the thermal expansion of chronium-base alloys"
Seminar on production mothodo, phyi;lcal proj\~rties, tuid electron structiwe
of refractory metals, compounds, and alloys, organized by the Institute of Powder
W-tallurgy and Special Alloys AS Ukr SSR, Klev, 25-29 April 1963.
(IL-plofizika vYso1Jkh temperatur, No. 1, 1,063, p. 1536)

3/2' 21610MM010OR101 P,/O 14
A006/A:101
AUT16W
Preparation of chromium chloride
PERIODICALt Poroshkovaya metallurgiya, no. 2P 1963# 88 95
TEU: A method of preparing chromium chloride is proposed which yields
metal with a low content of gaseous and metallic impurities. The method consists
in chlarinating ore, chrome oxide, or chrome metal with subsequent purification
of the product by Olatillation In a chlorine current, and reduction with mag-
nesium. Chlorination of Cr oxide was conducted at 950 - 1,00&C for I hour, and
chlorination of electrolytic Cr at 595 - 6050C for 50 min. The reactor cap&-
citor was coated with Asbestas at the spot where Cr chlorides were deposited;
this made it possible to maintain a temperature in the capacitor (500 - 60DOO
exceeding the melting point of volatile chlorides but not attaining the melting
point of Cr chloride. In such a manner only pure Cr chloride was deposited In
the capacitor. Me Cr-chlorides obtained were purified at 900 - 950"C by dia-
tillation in purified chlorine current. A spectral analysis bf Cr chlorides
Card 1/2

S/226/63/000/002-/012/014
Preparation of chr omium chloride A006/A101
-obtained from Or oxide and electrolytic Or -shows that high-purity chlorides can
thus. be obtained. The magnesium-thermal reduction of Or chloride was performed
~n purified helium.' Efficient reduction takes place at 65000 when magnesium is
melted, and shows an explosive nature. The reactor was held at this temperature
for 15 min; the temperature was then elevated to 8500C. Magnesium. chloride and
magnesium was eliminated from the crucible by malting and distillation in a
vacuum during 80 min. Almost 10%, Or was extracted from the chloride in the
form of gray powder containing not less than 99.96% Or. The interaction betieen
Or chloride and magnesium during thereduction process was studied and Is ex-
plained. 7here are 5 figures.
ASSOCIATION:, Institut metallurgii All 033R I Institut metallurgil im. A. A. Bay-
kov AN SSSR (Institute of Metallurgy, AS GSSR, and Institute of
Metallurgy imeni A. A. Baykov, AS USSR)
SUSW=: April 14, 1962
Card 2/2

4
ACCESSION NR: AT4013921 S/2659/63/010/000/0015/0022
AUTHOR; Ageyevt No Vol Modellj Me So
TITLE: Thermal expansion of chromium and solid solutions with a chromium base
SOURCE: AN SSSR. InstItut metallurgil. Issledovanlya po zharoprochny*m
splavam, v. 10, 1963, 15-22
TOPIC TAG,,-'?': chromium, chromium heat expansiop , solid solution, chromium solid
solution, Isothermal curve, chromium solubili y, thermalexpansion, elasticity.
elasticity modulus, roentgenography
ABSTRACT: One of the most important problems in the preparation of heat-resistant
alloys is to increase the strength of the atomic Interaction between the metal and
the base. The present Investigation used the voentgenographic method to measure the
coefficients of thermal expansion of chromium (the metal with the best possibilities
for heat-resistant materials) and of its solid solutions with molybdenum and vana-
dium. Figure I of the Enclosure shows the dependence of the modulus of elasticity
on the content ofonolybdenu .n solid solutions of Cr-Mo and the isothermic curve
of the coefficients of thermal expansion of these alloys. The modulus of elasti-
city of the Cr-Mo alloys was measured by V. V. Kondratlyev. In the region of the
maximal increase of atomic interaction, the coefficient of therinal expansion is
Card 1/3.,

ACCESSION NR: AT013921
lowered about 10%, while the modulus of elasticity increases 5%. in comparison with
published data it is evident that for other tran sition elements such as iron and
molybdenum, a strengthening effect of minute additions has been found when they are
introduced into the 5olid solution. These values of the mechanical properties are
close to those of chromium. On this basis it can be seen that a study of the
strengthening action of minute additions is of interest. Orig. art. has: 2 for-
mulas, 7 figures,.and 2 tables.
ASSOCIATION: Institut metallurgii AN SSSR (Institute of Metallurgy AN SSSR)
SUBMITTED; 00
SUB CODE: ML
DATE ACQ: 27Feb64
NO REF SOV: 007
ENCL: 01
OTHER: 006
Card 2/3---

FNIk Seminar on refractory metals, compounds, and alloys (Kievi,, Pril 19b3).
SOURCE: Atomnaya energiya, V. 15, no. 3, 1963', 266-267
ACCESSION NRt AP3008085
Ya. A. Kraftmakher. Heat capacity of W. Ta. and Nb.~'.
..'-V. M. Amonenko and others, Expansion coefficients of'Zr, Nb# He-#
'Ta, and W.
-!X!v, M. S. Model'. 'Expansion coefficients of chromium-base;
N... V.
aLloys
S. N. Llvov, V. F. Ne6chenko. Temperature depend 'ence of emf and
resistivity. of Cr', Ti, V,'an~d their borides, carbides, and nitrides;~:
Ettingshausen-Nernst effect in titanium, TiB., TiC, an'd TiN.
..N. V. Kolomoyets, The amf.of cfiromium-group metals and their alloys.'
G. V. Samsonov and o-thers. Superconductivity and thermal-electron,'
properties of refractory,compounds,
D. A. Prokoshkin and others.~ Magnetic, optical, and other 'properties
of refractory .elements and the- oxidation resistance of beryllides of
refractory elements.
Card 10/11

#~Vft;-40DELI, M.S.
Decay of solid solutions of niobium and titanium in chromium,
Dokl. AN SSSR 148 no,104-8f?'Ja 163. (MMA 16t2)
1, Institut metallurgii im. A.A. Baykova. 2. Oblen-l-orrespondent
AN SSSR (for Ageyev),
(Cb~omium-niobium-titatium a1loya) (Solutions, Solid)

-AQaML nagrazliden ordenom Lenina, dvin.Va
_AJ.4,q,.Iu
ordenami Trudovogo Krasnogo Znameni) medallyu za dob-
lestnyy trud v Velikoy Otechestvennoy voyne, otv. red.;
KURDYWOV 0 V akademik, red.; OD111G, I.A., red.
(deceasedi; ~,~~LIOV, I.M., red.; ZUDIN, I.F., kand. teklin.
nRuk, red.
[Study of stoehs tint, alloyn] 1.9oledovanila ,Aulai I
vov. Moskva, Nauka; 1964. 390 P. (MIRA 17:8)
1. Moscow. Institut metallurgii.2.Chlen-korrespondent
AN SSSR (for Odin, Ageyev, Favlov).

KORNILOV, Ivan Ivanovichi_A_qpEvj N.V....,otv. red.; FRIKLONSKIY, A.A.,
red.
[Metallides and their interaction] Metallidy i vzaimo-
deistvie mezhdu nimi. Hoskva~ Nauka., 1964. 179 p.
(MIRA 17:12)
1. Chlen-korrespondent AN SSSR (for Ageyev).

AGELYLV, 11.1J. , otv. red.
[Achievements of science arid teelmology: Metallurp.,
1962) Itogi nauki i tekliniki: .'etaalurgiia 11,162.
Moskva, Akad. nauk SSSTI, 1964. 347 P. (MIRA 1E:12)

7
L 156~8_65 EwT(m)/mYP(V0/ nWd)/ZVlP(_0/E T(b) ASD-3/AFftd/E
ACCESS!ON NR: ATLi,04680q S !ion /000/(,,O0l;/0009
AUTHOR: Ageyev, N.. _V. (Correspondi nc: memher aN SSSR) ~ mode I _M. S.
TITLE: The thermal expansion of solid solutions based on chromium
SOURCE: AN SSSR. Nauchny*y__~_ova p-o proble-ne zharoprochny-~rkh splavov. Issledo-
vanlya st_"~_Te_y-_T__ tud;es on stee's and 5 zd---vo Nauka,
5-9
TOPIC TAGS: thermal expansion coefficient, solid solution, binary alloy, chromium'
..ased alloy, crystal lattice parameler, microhardnes.5
ABSTRACT: The X-ray measurement re-,ults of the crystal lattice parameters and
the coefficients of linear expan~lon oi chroinium aiiovs with Fe, W. Nb. and T1
are d*-_,_-ssed :- detail. The allo~q ~,,re ~j ~j a twofold electrolysis,and
11)e !neit ;nq ql~, d.-me in a ;u~,penfjt- i ;,jrr atmosp,,ere, with
a r-adual hnmcqeni 7at ion annea i i nq d, 'Ed aF040n pressure. The
; e ~ ; 1 1 ; r. Q b ; n a -, a I I o y 5 wf~ r e s ~- ! : ,~ , r)a ~- ec,L, s d i 5 t r I bu t i on c) f
components. The dependence of th~- ~atti,e oorr temperatures or the
additive contert of the binary soi:d o- -3, Lorcent rat i on re9l ons
and the analogous dependence of t~ie a'lcv ~r;'~.rnna, c1r. e s 5 , E. r e s h own .Tj and Nb
showed the least solubility In chromium. The rma I expansion changes were also
Card 1/2

L 15658-65
ACCESSION NR: AT4046809
studied for the alloys Cr-Mo, Cr-V, Cr-W and Cr-Fe, whose lattice parameters were
measured at six temperatures (20-800-1. T,)e accurac,,~ o- t~)e lattice parameter
de!er-;nat10- waS ~-003,.. r~ r~t-, rjr-,,, ~, 1: -1 -p ,e
aqe t-~)C'Mal expan-
sion coeifictents were calculated with an accuracy of I-Z',Y,. The average thermal
expansion coefficients for Cr-Fe aliovs show that at admixture concentrations of
0.4-0.6 atoms %, there Is a friniawm on the curve. At greater contents of Fe, t e
coefficient is close to a for Dure chromium and Increases further. In Cr-V solid
solutions, the thermal expansion mininum occurs w;th an admixture content of
a b kx- t a t .1. In Cr-W a] love. , r~)P Parhprl ar a '%, concentrat ion
0t
Cj 6 . 4; at wh j i e Cr-Mo a i i ov5 snow a mi n I fraim at 0.,4-0~6 at at Mo. A iowering
F~ t ')e rma I e-;- pa n s 1 or :1 - with Mo, W V, and
F t 1,er--ta! expans: r
-)ci: n-~ a'- IC ene-Qv
of chrondurn
W, --a ,d ,~ mc,re roncer*rated
so4i4 sio-lutions 4 anb or. c,iariqes i n acc~ordarilce wl th the di f rerem-e
this therma-, i~p
ns "Coal- C I'd -:C rom nd-t kit-,
betwow- ff ar he We -
ti
to as i:,
re

1_-2_4320-~65 EP_V(z)-2/M' (=)/EUP(b)/EWP(t) Pu-4 A3D(w)-,3/AFTC(]p)/1JPt0
JD/,JG/MLK
ACCESSION NR: AT4o48053
5/0000/64/000/000/0058/0073
AUTHOR: Aqeyev, N. V.. Glazunov, S. G.; Petrova, L. A.; Tarasenko, G. N.;
Grankova,
TITLE: Stability of Beta alloys of the Ti-Mo-Cr-Fe-Al system
SOURCE: Sciveshchaniye,pci metallurgii, rneiallovedeniyu i primenen-iju.titana I y So
splavnv. 5t - - ~63. "a-a -"e~d'iccraphy of titanium);
MCI 5 __ CKW I ~ , I I
trudy-~ sove5h--hariiya. Moscow. lzd-vc N-3,1a, ~9614,
TOPIC TAGS: alloy structure, Beta alloy, alloy phase transformation, titanium
alloy, molybdenum alloy, chromium alloy. 1 r-~n alloy, alum:num alloy
ABSTRACT: Previous studies have shown the critical concentration for the 13-solid
solution of 3noth,?r element in ritanium tn he netween 6 and 9'4, and that the most
t
stable of these combinations are for-ied by rhenium, nickel. ricivbdenum, and tuna-
,,ten. Recently, --here has been much interest in --ulticomponent alloys with the
m-etastabi e 7-st ru,:ture, whi c~, have h; gh ! e-.- (. oc.: -a E-at i i ; ty when hardened.
for these and iuther reasons tne autriz~rs t~., t:lc li-Aci-Fe-cr-Al Sys-
tem, both in its f3-phase and with an eye to choosing alloys for more detailed
experimentation. The samples chosen for experimentation had molybdenum in con-
centrations of wt. 2-8*m/, chromium from 4-9'~, iron from 3-81, titanium from 81-83%,
Cord 1/2

L
-~-ACCESSJON'- NR:'- _AT4WO53
and aluminum con,,tant -4t 3%. All samples but one were held at 200C for 100 hours,
ho_-r.~. Two saayi -iere also held at 300C
and that one wa, h-~ld at 200C fur ~14 11 1
for 100 hours; all the remaining samples disinteqrated. Four of them "isintegra-
ted with the precipitation of the W-phase, wh;ch lg,,tfd 1,10 hours longer; the
whicn had 2
others disinteorat.?o w; [h, the preclp- tat i,-)r )f rn- Samp I es
and 5)~ Ho di d not Jepencl, "or the td~ r' t :1 es , on t he ci)r res -
por,C. rl~ arnoin I ~ 01 chro!-,':urT. ~,n_, i : c, r s - led, The 5ampleb with
2% Mo had amounts of chromium decreasin-1 from 9.07 to 3.76% while the Iron In-
creased from 2.8 to 7.37~; thc amount ot chromium in samples with 5% Mo decreased
from 9.40 to 4.08~ while the amouni of iron increased from 3.04 to 5%. in samples
containing up to 5% each of iron and chromium, I or 2% more than 5% Mo did not
,~Ignifitcantly increase the stability of ti~-e --alloy, and the deiay In the process
of disintegration ~s hardly worth the cost. Orig. art. has: 2 tables, 23 graphs,
11 photomicrographs, and 4 roentgenograms.
ASSOCIATION: none
SUBMITTED. 15jui64- ENCL; 00 SUB CODE: M
NO REF SOV; 005 OTHER: 000
C a rJ 212

ACCEMIC11 n: AP4041).45 0/0020/64/156/00470769/P791
AUMOR: Ageyev, No. Y,'*# Glazunov, S. G.; Petrova, L. A.; Tarasenko, G. N.;
Grankdva, L. P.
TITIZ: Dislocations in the titanium - mo3,vl>den= - iron aluminum alloys
SOURCE: AN SSSR. Doklady*p w 156o no. 4p l964, 789-791, and insert facing 790
TOFIC TAGS: alloy dislocation, Ti Mo Fa Al., alloy,, chilled alloy microatructure,
.etching., electrmicroscopic atudy
ABSTRACT; By analyzing the structure of a quenched a - alloy of Ti, - Mo - Fe - Al..
,the authors have found precipitations having the appearance of "sticks". Sind I a
ya by T. 11. So - ' ;
11sticks" vere found earlier in quickly chilled Ti - 10% Mo allo ho
!field et alo (Acta Metallurgica .7., no. 6, 403,, 1959) who described them as regular
-arrays of etch holes caused by unstable groups of dislocations which are chAnged
:during cooling into a stabler not of aubgrains. x-ray diffraction pattexua obtaind
,by the present authors show no presence of a new phase such as titanium bydride.
.!It is pointed out that dislocations which are present idall metals., become a7par-
.ent only under favorable conditions of etching. Electi-omicroscopia study-of the
"sticks" Ww actually demonstrated that they we fo=ed by a series of little
Card 1/2

'ACCFZMCIN IM: AP4041145
,holes- Orig. art. hu: .4 figme.
Assoamcn: Institut motaLb"gu Im A* Ae B&ykova (Imt:Ltute of Met&Uu-.W)
'SUERETTED: O5Fab64 ENCL: 00
;'SUB CME: M no mw am: 005 OMM: '002

w
----- - - ---
ijp(c) '7.)/JG
ACCESSION NR: APS013155 UR/0129/65/000/OOS/0033/0035
569.295'71'2b'28:621.795.74
A' 7,Hnp Gld~ ; Y
_~~e V ~L_v ~un~v S. G., Pe.lri~,va, L. A.; Tarasenko, G. N-
Gran~,ova, _11, P.
~ ~, ~1 1.
TITLE: Aging of 8-alloys -Cr~-Fe-Al'sys tem
in the T. o
SOURCE: Metallovedeniye i termiches~aya obrabotka rmetallov, no. 5, 1965, 33-35.,
and insert facing p. 24
TOPIC TAGS: ti'~anium alloy, chromium ailr_,y, rrY_-_!yh6enjrr, allov, aluminum alloy,
mtal physical property, metal hardnf:ss, metal aging
111
ABESTRACT: An attempt was made t~, find an ~Lging. ~,~~atme_nt which gives maximum hard-
-~,nesq an(,, streenjzth. A series ct! 6-FILC"'S were sele-e~ r-!- S"dying structure and
a f x, The Ti allovs in
of agi-~g
vestigated varied ~P. Composition:
A! (3.2-3.6%). A$er due processing and heat treatwnt, the alloys were examined
-dnesses were u*a3ur-ad. Both wtailographic and

1 Carl 114
L 57509-65
~ACCESSION NR:
APS013155
= .7,,* cp vp-n in
-V
fig. 1 of the Enclosure. The alloys were aged, after Drier annealing and treatment,
for one hour at Leq)eratures ranging from 30C ,., 110,Ducl.
-he hardness shows a
maximum around 500-~SOIC depending )r; the alloy. ~-)C-BCOIC t~)e hardness grad-
ual1v ~iminiahes, and after 8000C an insignificart increase .;s noted in some al-
--;s - A11 of the allovs ha-vT B-sol.d slruC7,,nes w:)e,) aged at 300 and 400'C,
r~ixt,~r-_ of ri+ 6 i:; noted after az niz Lii-ve 'he incma--;e in

IASSOCIATIONi none
SUBMITTED: 00
NO RFF SOV: 001
Cara
I:NCL: 07
wo
SUB CODE! MM

X - c
ACC NRs AP5026360 SOURCE CODEt UW0370/65/000/00S/0134/0W
ly 55 1 q 5-5
AUTHOR: Ageyev, N. V. (Moscow); Novik, P. K. (Moscow)
ORG-. none
TITLE: Effect Of aluminum the stability'of the 0-pbase in Ti-Mo-Nn lays
T?"MV,
'Iyla' y
SOURCE; AN SSSR. Izvest Hatall, no. S, 19659 134-138
TOPIC TAGS: alloy, titanium base alloy, molybdenum alloy, manganese alloy, aluminum
containing alloy, nonfer!rous metal alloy, metal testf alloy composition, alloy phase
diagram
ABSTRACT: The study examined the effect of aluminum an the stability of the 0-phase
in Ti-Mo-Hn alloys. Prior to testing for stability of the 0-phase, the alloy samples
were forge wprked at.1223-1023OX to thin plates, vacuum soaked for 2 hours at 11730K
and cooled. A in tests were carried out at 573, 673, 773, and 8730K. Test duration
varied from 15 minutes to 100 hours. The Hn + Ho contents in the alloys were 20-24%,
16%, and 12-13%. Tlub. study encompassed the following alloys: Ti-10Hn-12Ho-IJU,
Ti-10ft-12ft-2A1, Ti--l0Hn-3Al,, Ti-7Hn-9Mo-lAlj Ti-7Mn-No-2A1, Ti-7ft-SHo-W9, Ti-3.2
Hn-9.5Ho-lAl, Ti-3.211n-9.5ft-Wj and 11-34Hn-9.5&P-4A1. In Ti-HO-Mn alloys* the
stability of the 0-phase increased sharply in proportion to increases in the Al con-
tent (from I to 3%). ror alloys containing 16% of Mo + Hn, the introduction of 1% Al
suppressed the formation of the metastable w-phase. In the case of alloys containing
UDC: 669 495.5128174171.017.3

ACC NRs APS026360
.12-13% of Mo + Mn the introduction of 1 .or 2% Al caused a sharp reduction in the w-
'-phase concentration at 6730Ks and -the introduction of 3% Al eliminated the formatic
of the L-phase at 15730K 14 It was found that the presence of Al in Ti-Mo-Mn alloys
inhibited the diffusion1proce6ses in alloys and the decay of the O-phase, increased
the length of the Ud-uction period, and prevented crystallization in the W-phase, It
vas recommended that the development of commercial. alloy reinforcing by mans of
stabilization of the O-phase center on Ti-Mo-Mn alloys containing approximately 18%
(Mo + Mn) and 3% Al. Orig. art. has: 2 figures, 2 tables,
SUB CODE: 1l/ SUBM DATEs 14May64/ ORIG REF: 002/ OTH IREF:' 001
Card 2/2

(d.)/T/E,WP(1.- )AP'jF(n)-2/FWT(b) (c
ACCESSION NR- AP5013117 UP/0370/65/0001002/014
669.295 Vk
ALTMOR: G, (Mosciyw); Petrova, L. A. oscaw)
jgeXev 14 V (Moscow); Glazunov, S.
Tarosenko, G. N. oscow); Grankova, L. P. (Mc,s,--,,w)
TITLE: Hot hardnessAn 6 allcys of thp
SOURCE: AN SS;T?zvestiya. Metally, no. 2, 1965, 1411-146
TOPIC TAGS: -:jtaniuTi~. lloy, inolybdenum alloy, chromiiur 3111cy, aluminum alloy,
iron alloy, metal mechanical prcpLrty
ABSTRACT: Ho t hardness measurements on si x Tl'-Mr~-r-r - FP -A' ;il, -,;r vave a I-re m-* -
narw -; Je a of the ove r -al I h i gh. I ernr~e ra t ur- s, r~ 1~ ~keac,Arement~z were
er h~,I'd rg f
the 20-10000C riinge (aft i -,,r rine -,Ir.,;!e zk:t-~ versus timo
71c,tF 15, "r, rrin~-;tfs) we-e al~;'- ~"r -,ridcr a load
cf 1 Kg. Differences In positi:,ns of maximurr, nardness fcr the forved at 1000'C
vut nct reheated to 70CIC specimens is sa-id to bie causeul by aw difj-4.-r4.ut -=I
on.1
of a segregations,, - Allo 0 )n 'N
y.coV sitions used-had somewhat varying compositl( s.
.1heat-treated (forged) alloys maintained a higher hot hardness than heat treated al-'
J_Card 1/2

,Card 2/2---- --- -- -I - -- - - --- - - -- - - - --. -

AGEYFV, N.V.; GLAZTINOV, S.G.; PFTROVA, L.A.; TARAt-,FNKO, G.N.; GRANKOVA, L.P.
Aging of fi-alloys of the system Ti - Mo - Cr - Fe - Al, Metalloved, i
term. obr. mt. no.5:33-35 ~ly 165. (MRA 18t7)

, AGEEV~ ,N.V.
Nature of metallic phases. Izv.AN SSSR.Neorg.mat. I no.10:1629-
16314 0 165, (MIRA 18:12)
1. Institut metallurgii imeni A.A.Baykova, Moskva. Submitted
ALLy 5s 1965-

AP6036757 SOME COM UR/0020/66/171/00110077/
AUTHM Ageyev, No V. (Corresponding member AN SSSR)! Ivanova, V, So; Petrova, L, A,j
Ku d ry s M 7 V. W 5~5-nk o y~~, L . P
OR01, Institute of Metallurgy im. A. A. BnykovAN SSSR (Institut metallurgii
Akademii Nauk-SFS0Y
TITIX: Effect of structure on the -resistance of 0-titanium alloy crack eropagation
SOURM AN SSSR. Doklady, v. 171, no. 1, 1966, 77-80
ronium containing alloy, iron containing'
TOPIC TACS. titanium. molybdenum a I
alloy, aluminum containing alloy, #*&Weat treatment all r1ltTIMT-Gitoy
'-f all
/IV7
ABSTRACT., Specimens of IVT-1 0-titanium alloy of optimum composition (7% No,
5.5% Cr, 3% Fe,. and 31 Al) were solution heat treated at 800r (the'0-region), watr
quenched, and aged at 450C for 50 hr, at 500C for 20'hr, at 525C for 15 hr, or
500C for 15 hr. Microscopic examination showed that docnmposition of the 0-sr
solution became zm)re uniform as the aging temperature increased. After agiv
525C for 15 br, the alloy structure consisted of the S-solid solution Mat-
uniformly reinforced with a-phase acicular fibers 2 v or more lonp with
about one order lower. Similar precipitated a-phase fibers within 0-grL
their boundaries were also observed in the alloy aged at 550C for 15 hr.'--\
Card UDC: 669.295.5:620.17
1/2

NR# AT6012374
AUTHORS: Ageyei~pj. V.;. Glazunov, S. G.; Petrova. L, A.s Tarasenko, G.,N.j Grankovai-I
ORG-. none
TITLEt. Investigation of alloys of the system Ti--Mo--Cr--Fe--Al
SOURCE: Soveshchaniye P0 metallokhimii, metallovedeniyu i primeneniyu titana i yego
splavov, 6th. VoWa issledovaniya titanovykh splayov (Now research on titanium
alloys); trudy soveshchaniya. Moscowt Izd-vo Nauka, 1965? 89-91
TOPIC TAGS- ii 'tanium iron, chromium, molybdenum, aluminum, titanium alloy# metal
aging, annealing, haraness, x ray B ectrum / P
ABSTRAOTt The-effect of annealinXd aging on the hardness.and x-ray spectra of
alloys derived from-the system Ti--Mo--Cr_-Fe--A1 was studied. The experimental
procedure was described earlier by N. V.- Ageyev. ai-d L. A. Petrova (Dokl.1AN MR,
1961, 138, No.*2, 359). Five different alloy-cow., , '~L.tinw were studied, and the
experimental,results are presented graphically 1). Photographs of polished
sedti6ris-of the alloys-ann.ealed at different op and aged foiz different
.periods of time axe pres ented. The presence of m-tallite lines in the x-ray speatro-~~,
grams are noted, but the authors refrain from Diving an explanation forItheir pre.senc'e.
It is concluded that the alloys may prove interesting as low-alloy-A -stabilizing- -
high-strength titanium alloys.

~ACC NRI AT6012374
jog
-too
too I
#DO
JAU
9 to V Jo 15 Ix
I .- -_ ... I .b
Time fhours
Fig. 1. Hardness of alloys asa funotion of the temperature and duration of
aging. Aging temperature in Ct I - 350; 2 - 400; 3 - 450; 4 - 500; 5 - 5501
6 - 600. (a) alloy IT (2.9% Fe; 5-375 Cr; 1.47 Mot 2.53 Al; 0.020 C; and 0.025 X);
(b)-alloy 5T (3-01% Fe; 7,7 cr; 0-7 Mo;-i.2 Al; 0.016 C; and 0.021 H),
Orig, art, hass I table and 5 figures.
Card 2/2 6L& 61W CODEt 11/ SUM DATEt 02Deo65/ ORIG REFs 004
Hvt k mm
Y 2

F-ACC-MR, AP6016583
SOURCE CODE: UR/0129/65/000/005/0012/0014
.AUTHOR,. Ageyev, N. V.: Glazunov, S. G.4 Petrova, L. A.: Tarasenko, G. N.; GrankovaA
L. P ; Sh-61617-AT -T6 7'"
ORG: none
TITLE: High-temperature thermomechanical treatmen of $-alloy of the Ti-MO-Cr-Fe-Al
system r %171 T1 T~ 1, 1
SOURCE: Metallovedeniye i termicheskaya obrabotka metallov, no. 5, 1966, 12-14'
TOPIC TAGS: thermomechanical treatment, titanium alloy, titanium beta alloy,
.molybdenum containing alloy, iron containing alloy, aluminum containing alloy-, alloy
thermomechanical eatment,'alloy mechanical property, alloy structure
ABSTRACT: Forged\specimens of complex titanium-base alloy containing 7%Mo, 5.5%Cr,
3%Fe, and 3%A1 wer subjected to high-temperature thermomechanical treatment (HTMT)o
rolled at 850, 950, and 1050C with a 20, 40, and 60% reduction in one pass and 802
in two passes, immediately water quenched, and then aged at 450C for 15 and 25 hr,
at 500C for 5 and 10 sir, or at 525C for 5 hr. HTMT increased alloy strength without
affecting ductility. For example, prior to aging tiie tensile strength of alloy hot
rolled at 950C with a reduction of 20, 40, 60, and 80% was 96.5, 105.0, 96.7, and
99.5 kg/mm2, respectively, compared with 77.3 kg/mm2 for alloy quenched from the
sametemperature without deformation. The corresponding figures for elongation were
I

1 -2 ft 02 - 6 6
ACC NRi -'AP6016583
16.-6. 18.4, 17.7, and 18%, respectively, compared with lk.9%. The increase4 strength
of the alloy after Mr, is explained by strain hardenin I~knd fragmentation of the
O-alloy grains. Aging produced a fur_~her significant increase of strength. The best
combination of strengtli and d
A!Lc~ ~as obtained after HTMT with 60-80% reduction
at 85-OC and aging at 500C for 10 hr or 525C for 5 hr, after which the alloy had a
tensile strength of 164-177 kg/mm2, an elongation of 4.5-M%, and a reduction of
area of 8-15%. This effect of aging was found to result from the precipitation of
the finely dispersed *-phase. Orig. art. has: 3 figureD and I tpble.
SUBCODE: Il/ SUBM DATE: none/ ORIGREF., 008/ ATD PRESS:
Card 2/2

ACC NRI AP6019834 (IV SOURCE; CODE: UR/0370/66/000/001/0139/0148
AUT11011: ~goXov; N. V. - (Moscow); G~azunovj S. G. (Moscow); Petroyal L. -Afi Nolscow);
Tarasenko, GrankovaA- t. I?. (Moscow) 3
ORG: nono
TITLE-. Investigation of mvtastable 0-alloys of the Ti-Mo-Fe-Al system
SOURCE: AN SSSR. Izvestlya. Metally, no. 1, 1966, 139-148
TOPIC TAGS: phase analysis, quaternary alloy, titanium base alloy, molybdenum, iron,
aluminum, metal aging, mechanical property
ABSTRACT: This is a continuation of previous investigations (Ageyev, N. V., Rogachevskaya*,
Z. M. Zh. neorgan. IdAmii, 1959, IV, vyp. 10, 2323-2328; Ageyev, N. V., Grankova, L. P.,
Novik, P. K. Dokl. AN SSSR, 1962, 146, no. 2, 351-354) with the difference that it deals with
Ti-Mo-Fe-Al alloys which quench to the f~-solid solution, i.e. have an electron concentration
of more than 4.20 el/at, but contain not more than 8.5% Fe and 8% Mo as well as 2.3 and 4%
Al, and hence are of greater practical interest. Ingots of these alloys were melted by using
a mixture of titanium sponge AI-Mo master alloy, pure Al and armco iron. The ingots,
R
UDC: 669.295

L 44354-66
ACC NR: AP6019834
weighing 400 g, were lathe-turned and subsequently hot-forged in an electric furnace at
1000-IIOOQC into rods of 15 mm diameter and squares measuring 15xl5 mm. The forged alloys
were annealed at 750 and 8000C for 1 hr and water-quenched. All the alloys quenched from
750*C had the 0 + ce phase structures, and all those quenched from 800*C, the structure of the
0--solid solution, as was to be expected from their electron concentration. The forgings were
milled in a milling machine and cut up into specimens for microstructural and radiographic
examination as well as for tests of hardness and tensile strength. Measurements of the Vickers
hardness of these alloys as a function of aging temperature (200-600*C) and time (1-100 hr)
revealed that for most of the alloys hardness reaches its maximum (-500 kg/mm) after 10-25
hr at any aging temperature within the limits considered and thereafter remains virtually con-
stant for 100 hr. ~-alloys containing 2% Al, when heated to 400-500*C, undergo decomposition
with segregation of w-phase which gets transformed into a-phase after 10 hr. 0-alloys contain-
ing 3 and 4% Al undergo decomposition with segregation of ct-phase. Of the alloys of Ti + 7%
Mo + 6% Fe + 2,3 and 4% Al the best mechanical properties (tensile strength 160 kg/mm2,
plasticity 7. 0%) were displayed by the alloy with 3% Al aged at 525*C for 20 hr and subse-
quently cooled in air. Orig. art. has: 7 figures, 3 tables.
SUB CODE: 11, 2k 13/ SUBM DATE: 02Mar65/ ORIG REF.- 005/
L(Lard 2/2 b1g

ACC NRt AT6034440
AUVORI Ageyov, N. V.; Models, X. S.
CRG: none
TITLE: The effect of small additions and impurities on the lattice constant and
thermal expansion of molybdenum
SOURCE3 AN SSSR. Institut metallurgii. -017~;.11-4,va i primeneniye zharoprochnykh
r-plavov (Properties and application of heat resistant alloys). Y45cow, Jzd-Vo Nauk&,
1966, 93-98
TOPIC TAGS: molybdenum, crystal.lattice, thermal expansion
ABSTRACT: The article reports measurement of the lattice constant of metalloceramic
molybdenum and an evaluation of its change with different degrees of refining. The
samples were prepared by 'are malting in a vacuum, by melting in a suspended statel by
zone refining, and by electron beam melting. The lattice constants were measured by
reverse exposure with flat, massive, and powder samples. Spectrally pare gold was
used as the standard. A table, based on the experimental results, gives the values of
"he lattice constants for molybdenum of different purities, It was found that
annealing at M00C completely eliminates the stresses. The dept)i of the hardened
layer depends on the method of working the surface; in the given case, it was of the

ACC NRi Al"(002403 SOURCE CODE: UR/0-30[WXUZTUX-~~~-
tAUTHOR: Alekseyevskiy, N. Ye.;,Mgev, N. V.; SbamraY, V. F.
ORG: Institute of Metallurgy im. A. A. Baykov Academy of Sciences SSSR (Institut
Imetallurgii. Akademii Nauk SSSR)
ITITLE: The critical temperature of the transition to the superconducting state of
the 6-phase in the Nb-Sn-Al-Ge system
jSOURCE: AN SSSR. Izvestiya. Neorganicheskiye materialy, v. 2, no. 12, 1966,
2156-2161
!TOPIC TAGS: niobium ing alloy, germani= containing
,alloy, superconduct, ansi-t-ion-temperaturel-alloy transi-
iti,en temperature
ABSTRACT: Beta-alloys of the Nb-Sn-Al-Ge system with vario .us.contents of the alloying
elements were levitation melted from 99.8%-pure niobium and 99.9992-pure
aluminumi tin and'germanium, homogenized at 600C for 250 hr and water
quenched. Nb3Sn, Nb3A1 and Nb 3Ge compounds were,found to have a temperature
of transition to the superconducting state (Tcd Of 18-1, 17.4 and 7.lY,,
respectively. With increasing Sn content-in alloys of the pseudobinary
Nb3Sn-Kb3A1 section, Tcr gradually decreased, reached a minimum at the Sn:A1
ratio of 1:1, and graduilly increased again with a further increase in the
Sn content. In alloys of the Nb3Sn-Kb3Ge section, T dropped sharply with
cr
L-Card .1/3

ACC NR$ AP7002403
1 an Increase of Nb3Ge content to about 70%, and then remained almost constant.
Al -Nb Ge
With small increases in the Ge content of alloys along the Nb3 3
section, T slightly increased to a maximam in alloy with a 4:1 Al:Ga
an
ratio, andcEhen decreased continuously with increasing Ge content. The
Fig. 1. critical teaperaturas
(K*) of alloys of the-
Nb3SU-Nb3Al-Kb3Ge section
.17Z
14Y
f
LIP
k:"
OR Pq 0
jig/
'W
Card 2/3

-4CC NRt
AP7002403
composition dependence of Tcr in the Kb3'Sn-Kb3Al-Kb3Ge section is shown
in Fig. 1. The critical temperature Tcr was also found to increase with the
increasing degree of ordering of the investigated alloys. In the Nb-SrL-Al-Ge
system, the value of T appears to be determined mainly by
cl .the, density of
states at the Fermi our ace. Orig. fiit- h":''' I-Tigures*

ZAGR'UDNYl, Ivan Vasillyevich, inzh.-mekhanik;
.... L~
GONCHAROVA, Ye.A., tekhn. red.
(How to obtain high productivity fror, earthmoving machinery]
Kak proizvoditellno ispoltzovatt zemleroinye mashiny. Bel-
gorod, Belgorodskoe knizhnoe izd-vo, 1961. 42 PO
(MIRA 15:2)
(Earthmoving machinery)

XOTELINIKOV, Boris Pavlovich; DOLYA14OVSKIY, Dmitriy Mikhaylovich;
AGE YEV P-,-M,.,-.red.,- GONCIWIGVA, Ye.A. tekbn. red.
(First in the country; story of the Shebekino Combine of
Synthetic Fatty Acids and Aliphatic Alcohols]Pervyi v strane;
rasskaz o Shebekinskom korbinate sintetichesk-M zhirnykh kis-
lot i zhirrWkh spirtov. Belgorod, BeIgorodskoe knizhnoe iz~-
vo, 1961. 49 P. (MIRA 15:8)
1. Direktor Shebelcinskogo nauchno-issledovatellskogo instituta
sinteticheskikh zhirozameniteley i royushchikh sredstv (for
Kotellnikov). 2. GlavMy inzhener kombinata sinteticheskikh
zhirrqkh kislot i zhirrWkh spirtov (for Bolyanovskiy).
(Shebekino--Oils and fats)

V V ok 1, 10 to I
otI Ol ; i i I I t", I
!

0
%
yok
00.
00
..00
to ) 0
.4 (
0

to f 11
Ath 0
f to
al." ti. N"
o
mots'
aid am' d- V~ "OullcIll
VIC
N I
&
lc
w
l
i
ot%lLnddect'~
W-trudts
00 ca
'be '
h
r
b
t
L itictc,",
f
~, bcsinnillS 1,
llwall"
09 %) itai
tki'mid. Nv
t roe
00 a Its t ro
00 0
00
00
go we 0
0
too
0 z :too

0 CL.SSIFICATIC"
00 j
-
Of
it
Z.0
mm,,
0 0 0 0
it 00
A
4 : 0 0 0
0 090
v

u
0
0
0 0 a
0 00
A
0 s 0
0 0 90
ee* 0
0 0
*go 0 0 a
0

--06
surei; to the production at 5teel. 11. Yd.
M 101K16). Steel rimij, C 11,111 0A WKI 1)
Ul4-0AWV,,~ was TnOtrA in an imhaction fume unck-Sr A
11SCMUC 01'.(P ~ji Joint, Jig. t)%ing SO WAC6011 1AIth C IhC
J)conirtit was rr0w&d toO. X)*', SmowoflbcC
It n'dtKvd N" opflw Xto) 01116 m1wilile. If. W. R. ere
zoo
co
goo
go
00
too
ISO 0
;we*
Ile it,
S; off
1ki it tv SO a is Do Id 111 A I W It it It K
0.0
0
to
9

POCCIMS AND Pac.141,1S
on dw Kills" of RawUm in fiti ProducHm of fteil. .00
P. V&, Ageev. (Metallurg, IM, No. 2. pp. 3-15). (In Rumian).
00 1 7%-0-allihor'-points out that fichenck's fortnuls, for the mte of oxide- -00
gel tion of carbon according to the equation PeO + C:;*- CO + Fe .00
"III open-hearth and elwWo furnaces is not in accordance with the 'Ies
true state of affairs and dom not explain some rmults actually
00 1
observed. It in suggested that the mathods of chemical dynamirit
ISO f 0
(the exponeintial rate of reaction involving the ides (if reaction
e0 only between activated mcileoules) should be applied to reactionx 090
00 oc-~ff in the strol-malting proom. It Is shown how the equa. =40
t,.= rlived will explain such ob~wved facts am the differenwe in' 1300
00
the rates of carbon removal from melts with originally equal carbon
00,
and oxygen contents uld th conalste ti slightly higher niuvpn
eel content of eleotric-furnaft L oom; =n with opo~.hearth steel. roe
The nwhankm of the activation of molecules Is considered. Since
the activation of molecules leads to nion rapid reaction and the
more rapid oompletion of the promme involvul in the produrtion
of bwel, it would appear that the electric-mv furnaet, with it-H age
enhanood aeurating oonditions is to be favoured. Attouipts to
otlow down rates of reaction in are furnarm to the level of thow 9041
in open-hearth furnactis are miquided. we*
I
*ITALLVUXAL LITIROL41. ClAjtI?IC&T*g
use
Iaw III-all
so
igloo) ;411 G%V 001
fill Ica ONY r1j-
IF 0 1 0
q-j:- 'A .10 uniti itan 1(11 (1 IV 14 PA 3 Il V_ 00
0 e 0 66 '00 9 Is 0 0 0 0 60 0 0 a d"
0 0 0 0 0 0 0 0 6 0 9 0 0 0 1~* 0 0 0 0 0 0
000

RO
of;:,rf&cv,,phvnamena in the development of pso(
La
acuon. 11, l'0. '!F1 V.
go
3id 1044, 14' '.0. I'lit p!i.t, III,- I,
"IIIIII1,11R)II Itillf
11111.1 far'. willit-Ill I, III is 1) v dJ. G. M. K,
14 i
a ,
'1~9 9
TOO
-.2. too
too
-7A
u it AV 10 '1%
S n (I tt IT a cc t( ft 41C
0 * 0 0.0
, ~6016 a 0 o0 010 o 0 0

IM'It'411111ort .
"106U Jun 1947
steel, Mqftld
*Pbyaioa'l and Chamical Processes In Liquid Steel,"
P. Ya. Ageyev, Candidate Tech Sci, Leningrad Polyteob
Mast, 5 pp
"ftal'N No 6
L2vestigation or physical atd chemical processes
Vh1ch occur in liquid metal, particularly those con-
camed vith generation of ncrawtallic additlons,
permits an examination of formation of properties or
steel; espeoially first stop, vhich depends on con-
tent'af additions. To solve these probleims, it Is
necessary to troaden studies of surface tam Ion on
58M
(Contd) J%M -1947
llqald metal-a. product of chemical reaction, -*and to
wcwk oat a method for evaluating this important
factor In metallurgical processes.

Ageyev. P* Ya. - "Determining the dif fusion coeff icient of ferrous oxide in slig,
Sbomik nauch.-takhn. o-vo meta.Uurgov, leningr. otd-niye), Issue lo, 1949, P. 22-
31, - Bib2Aog-. 7 item
SO: U-524o, 17, Dec. 53,(Ietopis 'Zhurnal lrq*h Statay, Vo. 25, 1949).

IGZ,lzv,-Pja.; ILABYSHRV, I.F.; BAYMAKOV, YU.V.; MLYAYIV, A.1 *-;
'- bdfAREV, L.A.; VASILIYEV, Z.V., GUPALO, I.P.; GUSIKDV, Y.M.; ZHURIN,A.I.-,
YETYUKOV, M.H.; KOSTYUKOV, A.A.; LOZHKIN, L.N.; OLIKHOV, N.P.;
OSIPOVA, T.V.; PXRTSEV, I.I.: RU14YANTSF.V, M.V.; STRELETS, Ye.L.;
FIRSANOVA, L.A.; CHUPRAKOV, Y.Ya.
Georgii Alekseavich Abramov. TSvet.met. 27 no.2:72-73 Mr-Ap 154. 1o:10,
(Abramov, Georgit Alekseevich, 1906-1953)

137-1958-2-2355
Translation from: Referativnvy zhurnal, Metallurgiya, 1958, Nr 2, p 22 (USSR)
AUTHORS: Suchil'nikov, S.I., Agevev, P.Ya.
TITLE: Irvestigation of the The'rmionic Properties of Steel-smelting
S3- ilssledovaniye termoelektronnvkh svoystv staleplavil'ilykh
s'... _jv)
PERIODICAL: V sb.: Fiz. -khim. osnovy proiz-va stali. Moscow, AN SSSR,
1957, pp 453-463. Diskus. pp 505-512
ABSTRACT: Methods are described for measuring the emis5ion current at
temperatures of appx. 16000. A study was made of slags containing
CaO and Si02, CaO, SiO? and A1203 and of four slags from electric
reducing furnaces - It was found that the work-function potential
depended on the CaO:SiO2ratio. It was noted that, as the SiO? con-
centration in the slag increased. the emissivity of the slag decreased,
whereas the work-function potential increased.
Yu.N.
1. S3.ags,%'lectrical properties
Card 1/1

DOROVe
N.F., kand. tekhn. nauk; MIMYIA)Vj, O*A*, kand. tekhn. nauk;
FZLIDWg I.A.; DANILOV, A.M.,- SORCKIN, P.Ta., kand. tekhn. nauk,
starshiy nauchnyy sotruinik; BUMOV, DZ,,, kana. tekhn. na*,,
clots.; SOYM. V.M.; LkTASH, Yu.V., m1adshiy nauchnyy sotrudnik;
ZAMOTAYIV, S.P.; BRYTEIIHAN, A.Ie; SAFKO, A&Ie; flFTU OVg, GeKeq
kand. tekhn. nauk; YON"RRAL, F.P., kana. t!3khn. nauk, dotB.;
UPUILYMIN, N.M., kmd. takhn. nauk, starshiy nauchnyy sotradnik;
ROZIN, R.N.; NOVIK, L.H., kand. tekhn. nauk, starshiy naudbx~7
sotymd-mik-, L&VRXNTIYYV, B.A.; SHILYAYNT, B.A.; SHUTKIX# N.I.;
GNUGHB79 S.A.,'kand. tekhn. nank, starshi7 nauehn~7 aotrudnike,
LYUDD(AN, K.F., dok-bor-inzh., prof.; GMJZIN, V.G., kand. tekhn.
nauk; BARIN, S.Ya.; POLYAKOV, A.YV., kand,tekhn, nank; YMCH3M,
A.I.-,4GAYK7Oj?.Ta., prof., doktor; SAMARINO A.M.; BOKSHITSKIY#
Ya.M., kand. tekl~i. na,.*-, GARNYK, G.A., kand. teldm. nauk;
MARKARYANTS, A.A., kar-d. tekhn. nauk; KRAMAROV, A.D., prof.,
doktor tekhn. nauk; TIM, L.I.; DANILOV, P.M.
Discussions. Biul. TSNIIGHM no.18119:69-105 157. (NM- 11:4)
I. Direktor Urallskocc instituta chernykh metallov (for Dabrov).
2. Direktor TSentrallnogo instituta informatsii ohernoy,metallur-
gil (for MikhaylcyT). 3. Nachallnik nauchno-issleaovatel skogo
otdela onobogo konstruk~orskogo by-uro tresta "31ektropG~;hlff (for
Felldman). 4. Nachallailk maxtenovskoy laboratorii Zlatoustovskogo
metallurgicheakogo zavoda (for Danilov, A.M.). 5. Iaboratoriya
protsessov stalevareniya Inatituta metallurgii Ural'skogo filial&
AN SSSR (for Sorokin). /- .. - -%

DMOV. X.F.-- (continued) Carl 2.
6. Urallakiy poljteWmiohe9kIy inatitut (for Butakov). 7. Starshiy
inEhener Rryanskogo mashinoatroitellnogo zavoda (for Soyfer).
8. Institut elektroavark! im, Patona AN UM (for Iatasb). 9. Na'.-
challnik TSentraltnoy zavodekoy laboratorii 'Uralmshzavoda" (for
Zamotayev). 10. Dnepropetrovskiy metallurgicheekly institut (for
Sapko), 11. Moskag-skiy inatitut stali (for Yedneral). 12. TSentrall-
nyy nauchno-isoledovatel'skly inatitut chernoy metallurgii (for
Gnuchev, Iapotyshkiz). 11. StnraMy master LeniWradskogo zavo&a
im, 11rova (for Roria). 114 Instita'd melvallurg-li Im. Baftova AN
SSSR (for Novik, Pblyakcr;r, Garnyk). 115. Nachallnik tekhnicheekogo
otdela zavoda "Bol Isherik" (for lav-zant Oyer). 16. Starshiy inzhe-
ner tekhnicheskogo otdela Glavapatsstali Hiniaterstva chernoy
metallurgii (for Shilyaye-7). 17. Zamestitell nachalinika tekhni-
cheskogo otdela zavoda "Ilektrestall" (for Shutkin). 18. Frey-
bergBkVa gornaya akaderdya, Germnskaya De-mokraticheakaya
Respublika (for Lyudeman). 113. Zavedikrashchly laboratoriyey stall-
W
nogo lit lvvL TSeutralgnogo nauchno-iseledovatellskogo instituta
takhnologii i mshinostroyaniya (for Gruzin). 20. Starshiy master
elektrostaleplavillt~d& pechey Uralvagonzavoda (for Barin).
21. Zamestitell nachallnika eleklurostaleplavillnogo tsekha zavoda
"Sibelektrostall"'(for Fedchenko). 22. Zaveduyashchiy kafedroy
metallurgii stali i elektrometallurgii chernykh matallov lenin-
gradskogo politekbacheakogo instituta (for Agoyev), 23. Zame-
stitell direktora Instituta metallurgii im. Baykova AN SSSR, chlen-
korrespondent AN SSSR (for Samarin).
(Continued on next card)

DUBROV, N.Y.--(contimled) Card 3.
24. Nachallnik laboratoril TSentrallnogo nauchnc-iBeledoratellf;kogo
instituta chernoy wtallurgii (for Bokshitekiy). 25. ZavediVashchiy
Icafedroy elektrometall-argii Sibirskogo metallurgicheskogo insti-
tuta (for Kramarov). 26. Nachallnik elektrostaleplavilinogo taekha
Kuznetakogo metallurgichoskogo kombinata (for Tedor). 27. Nachall-
nik elaktrometallurgicheakoy laboratorii Kuznetskogo metallurgiche-
skogo kombinata (for Dardlor, P.M. ).
(Steel--Metalluxgy)

AU,THORS: Chernc-4, B. G... Agz),o- so e. -
TITLE: Phy5--*--.a'-,. and Chsm-l %al Yanlamert~ -A' M,~"37. -,g
Gas Atmc-3php-rp (F-.zik-,~-khf-mf clleE;k:ay~.
zal
PERIODICAL: Nai;.rhnyye rl,-,k,ady -.yss~,2v shjkc-ly. Metaj'jj-g4.V '9% N-- 2;
PP- 43--49 (USSR)
ABSTRACT: The therretloal ba-=!..3 of thp melting methcds --f me-al SJr. vaz,.,-.~m
and pr-t-.ti-;(~ gas alm~sphera wpre disc.ussp,-d. In maltlng metql,;
lUnstating r-;f Armoo iron and oa-rb~~n
content of th-:~ metall J,, r',)t aff,~-eted by +he c,-ntent
during the melto The depend~-Tic~e be-~ween tb-? rltrogf~-,l ~~Dnoer-
tratinn a,-,d the ~~br,~niium flontent c-.f th- mal:ql. :[-,, :q:.uur.D mr'.1tij,g
wt-:~-p :'.nves t ".gated. From these --!.-r,-,rpqt-iga+4o-16 may 'op -4eer: ~~at
with an increase cf the -hTC'M4-"-IM ~:Llr.tP-; I. In +hp metal a dp-
cf the :ref"i.Ing pT~;--%ess of -the fir-:~m -r4.irrg-
In the me.'f-lng -f +h~-: a'-,':I.rys oc-c-ors. ThF~
ell-ipp.-AF3 in the mptals In their .1n
gas atincsyhF~::~ was :~r.-,esf`gated- It rs.3 -~hs' Wh-rl `t~
Card 1/2 melt.j.rg 1 ~ -arried -ut 4r, a

SOV11"61,
Physl;7al and Chem'--a" Y;rdamerts %f Y.?lr,' V!, ;,17 Ir"; P-
Gits Atinosphe:~--,
-f neu'ral gaa~--;
and 'fi--: -n 7f m9ta' 2 -f th~
::,-Ujp0F4 I--, C,~
h Trada ~.a5 i -::. Thz
and r,-' Ir,,gr-r nt ent r A:7m~- at ul! ff =ren.* arg,.~n. pre ;.5u-
were iri~.T~~it-lgatlpd. Mel-ts J-n argvn atm,~.,,Phe7e .7-ow press-uTp Ao
not 2aacl Ito a :iuffir-ient refining of the mqtals. There are
and ?
ASSOCIATION: LenlAngicidskiy pe-.JI-?khr~~'chfiskly
lyls+ Itu
SUBMITTED: 195"!
Card 212

_.T,_9.

pi.m... 0.... . ......

...... ..... a r.......a
a-

etaa..

R.A.Yropm 6140"Iss a tamayfalosamso eta-
ID.T.k.moto.-

...a. L
0. LD,.",

P- a- P.~
Z
... . ... Z
C. b.-

B,rLK pp.- s. . . se . . .
n-O.A:.* as. aowvoam~
fear m"Ical
"Pon on stool produotloo, 30 JM 19594

AErAmu'im cumi H CIIIIASOR

.%.A. __
tL,_
......... . . . .. . .
ILmr..-

r.moomm old"O"ll talva"'I two pro
AAMU~....

64ALA.- z 7
r Zc.-

ILX~_

...... ..... . .
S.H.C.P.6

T.M.5-
HMho.".
M: r-K.- 3OXMMA.
pM rubmitted ror Um 5th Mrleal Mnical
~.fv"rows an Oteal PrOwtIon, Nnecw-- 30 kn 1959.

8/137/6-i/ooo/m/ooi/149
A006/A101
AUTHORS., Ageyev, F.Ya., Karasev, V,
Shkarednyy, M.V.
TITLE: On the problem of deox1dizing sieel-with aluminum
PERIODICALs Referativnyy zhurnal, Metallurgiya, no. 12,-1961, 15, abstract
i2A84 ("Nauohno-tekhn., inform., byul. Leningr. politekhn, in-t",
1960, no. 11, 3 - 6)
TEXT: The simultaneous changes of 0 and Al content during deoxidation of
liquid 1~e with aluminum were investigated in a 5 kg laboratory induction furnace
with magnesite lining, Melting and holding of the liTaid metal were performed
in pure argon atmosphere, An amount of 0,_3% Al was added to the metal during
thorough stirring of thf~- pool with a quarxz rod. Ir all heats a sharp decrease
of the 0 content in the metal was observed immediately after the addition of Al.
At an initial 0 content as high as 0,03% in experimen"'.al heats, only about 10%
of the Al added are eliminated due to the reduoei concentration of 0 in.the
metal. Loeses of Al on account of Al oxidation on the pool surface did not take
place; at such an Al-concentration, evaporc.ion of Al is negligible, Los6es
of 40% Al, determined during the inveztigatlon, are considered to be caused by
Card-i/2

, 3/137/61/Wo/012/ool/149
On the problem of deoxidizing steel with alumintun Aoo6/*Alol
9
the interaction of Al with Fe oxides of the active layer of the furnace lining.
Within the first 6 - 7 minutes of holding the metal, the total 0 content is re-
duced to minimum values, during longer holding it does not change or increases
slightly; this occurs cn account of levelling the ra,e Gf 0 supPly and elimina-
tion from the metal. Establishing the constancy of the total, 0 content in the
metal at this moment does not correspond to an equilibrium state, since the Al
concentration varies continuously, The equilibrium s-late begins after more than
15 m4-nutes. The equilibrium constant of the d:~cxida-,lon reacticn of Fe with
aluminum in a magneBiie' crucible is eEtimatel ~o I-,e 1,,10-11-01,5 ~ 10-11.
Yu. Nechkin
[AbBtrac-ter's notex Complete translation]
Card 2/2

S11 37/62/`000/002/007/ 14,
A0061AI01
AUTFORS: Aj~gyev, P. Ya.,-Chernov, B, G.
TIME: Behavior of composite-alloyed alloy components during melting in
vacuum induction furnaces
PERIODICAL:' Referativnyy zhurnal, Metalliirgiya, no. 2, 1962, 17-18, abstract
2A84 ("Nauchno-tekhn. inform. byul. Leningr. politekhn. in-t",
1960, no. 11. 7-16)
TEXT, The authors investigated the behavior of components on NI-base
alloys with up to 10% Cr content. It was established that after melting of the
heat at a pressure as high as lo-3 mm Hg the Cr content decreased by 1.96%;
this is in a satisfactory agreement with the given calculations. Losses of
components in alloys, alloyed with Cr, Al, Ti, Co, W and Mo, were dQtermined in
a OKEI-497 (OKB-497) Induction vacuum furnace at 1; 5.10-2; 1. 10-.5 mm Hg
rarefaction degrees. The 0liquid metal temperature was measured with an immersiai
thermocouple and was 1,600 C for the majority of heats. The use of inert gas
during melting of the heat reduces losses of alloying elements to minimum values.
Gr content is subjected to maximum changes during the holding of the melt under
Card J/2