SCIENTIFIC ABSTRACT LIVSHITS, B. G. - LIVSHITS, B. G.
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Publication Date:
December 31, 1967
Content Type:
SCIENTIFIC ABSTRACT
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INLYITSUTA, I.S.; LIVSHITS, B.G.
Investigating the kinatics of phase transformations in X1617
heat-razistant alloys. IzT. vys. uchab. zav.; charns mat, no.1.
175-179 160. (MIRA 13:1)
1,Xoskovskiy institut stall.
(Heat-resistant alloys) (Phase rule and equilibrium)
85810
Sllh-@1601000100'1 14/1)18
1 2, ILI 1,5114'54 A 16 1 /.40?- 9
AUTHORS: Zakharov, Ye.K.; Livshits,-B.G.
TITLE: Allotropic and Magnetic Transformations in Cobalt-Chrome-Titmnium
Alloys
PERIODICAL: Izvestiya vysshikh uchebnykh 2avedeniy. - Chernaya metallurgiya,
1960, No. 3, PP. 125 - 130
TEXT: Allotropy in the Co-Cr-Ti alloys investigated was -determined by
measuring the magnetization of the alloys during heating and co:)1ing in weak
magnetic fields, using an improved Akulov AAr-5o (AAG-50) anisometer with a
more sensitive suspension on longer springs. This anisometer shows a 350 - 400mm
shift on the scale in 1.5 m distance during measurements on a 35 M long specimen
of 3 mm in cL-Lameter and a 150 - 200 oersted outer magnetic field. The position
of the light spot (shift) could be reproduced with -#1 m accuracy. The growth
of magnetization with allotropic transformation is @learly seen on levelled curve
portions. The improved anisometer is insensitive to building vibration and
traffic in close vicinity to the premises. Curie points were found with suffi-
cient accuracy in the 20-1,1500C range. The interdependence of Curie points and
the alloy compositions was found. The Curie points dropped In alloys with Cr and
Card 1/2
85810
s/148/6C)/000/003/014/018
A161/AO29
Allotropic and Magnetic Transformations in Cobalt-Chrome-Titanium Alloys
Ti; binary Co-Cr alloys with over 18-19% Cr became fully non-ferromagnetic at rcom
temperature. Some alloys had two Curie points, which Indicates a high tendency
to overheating and overcooling. The solubility of Ti in Co was stated to be about
8% at 850'r, and to drop with decreasing temperature. This nearly fits the value
of 7.2% found by Koester (Ref. 5), but Is far from the value of 20% folLnd by Liv-
shits and Khorin (Ref. 7). MIcrophotographs confirmed the magnetic measurement
results: beginning heterogeneity was found in a structure with 9% Ti, clear euteo-
tic in the case of 12% Ti; Co-Ti with less than 4% T1 had martensite structure
with Co in d-ani P-phases. Eutectold decomposition was observed at more than 8%
Ti rontent. No sign of martensite or eutectic was revealed In structures with 4-
-8% Ti, and It. appears that thesia processes are inhibited In this Ti-content range
In ternary alloys with Cr!.Ti-1 the structures sequence was analogous, and the
total solubility of Cr and Ti. at 7200C was 8% (4% cr and 4% 11). The high differ-
ence of data obtained compared withReferexe-7 will be discussed later. 'Arhere are
5 figures and 7 references: 2 Soviet, 3 German, 2 &glish.
ASSOCIATION: Moskovskly ins'ritut stall (Moscow Steel Insti-,ute)
SUBMIITED.- Febriary 27, 1959
Card 2/2
80Z.5
P. "XS--0 0
2 /.%S70
AUTHORS:
TITLE:
W148160100000510041009
Belyatskaya, I.S., Livshits, B.G.
.___ -;I V
The K-State and Durability of Nickel-Chrome% ase Alloys
PERIODICAL: Izvestiya vyeshikh uchebnykh zavedeniy, Chernaya metallurgiya,
1960, Nr 5. PP 99 - 101
TW: The K-state, revealed in a number of single-phase alloys, en-
tails strengthening of interatomic forces in the solid solution. Apparently,
the K-state impedes diffusion processes in heat resistant alloys, in parti-
cular, coagulation of the strengthening phase, and consequently may improve
their heat resisting propqrties. This was s@udied by continuous heating and
cooling of 3M437 (E1437)(tand 30617 (EI617)llalloys. To reveal the effect of
the K-state on heat resisting properties of E1617 alloy, specimen.3 were
subjected to standard treatment and preliminary standard tempering up to the
K-state (Table 1). Table 1 shows that tempering up to the K-state almost
doubles the durability of the alloys. The positive effect of the K-state on
the heat resistance ot E1437 specimens was established by cooling the speci-
mens and by tempering them at 70000 (Ref 71. Table 2 shows that delayed
Card 1/2
dAI
04S
S/148/60/000/005/004/009
The K-State and Durability of Nickel-Chrome Base Alloys
cooling down to 6000C increased the durability of the specimen. The experi-
ments confirmed G.V. Kurdyumov's theory on the effect of interatomia forces
on beat resisting properties. The K-state probably improves also the heat
resisting properties during intermittent tempering; this is explained by
the fact that nuclei of the OLI-phase, forming during cooling periods between
the tempering times, grow only slightly, since their coagulation is impeded-by
the submicroheterogeneity of the solid solution (K-state). This state arises
during the multiple cooling and heating processes and is maintained at high
temperatures. On the other hand the separation of the Ot-phase furthers a
fuller development of the K-state, since Al and Ti are eliminated from the
solution which becomes more durable during each cycle of tempering. This im-
pedes coagulation of the 00-phase. The use of tempering up'to the K-state
or the replacement of continuous tempering at 8000C by intermittend tempering
may raise the operational temperature or the admissible strain. There are:
2 tables and 7 references, 5 of which are Soviet and 2 German.
ASSOCIATIONs Mo3kovskiy Institut stali (Moscow Steel Institute)
Yxhv: June 22, 3.959
Card 2/2
jib
86070
S/180/60/000/CO5/011/033
EO?3/E535
AUTHORS. Belyatskaya, I. S. and Livshits, B. G. (moscow)
TITLE: On the Theory of Phase Transformati_on@in Refractory
VYC,C_iLei_Chromium Base Alloys
'."'n
PERIODICAL: Izvestiya AkaJemii nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivo,, 1960, No.5, pp.122-127
TEXT: The authors investigated phase transformations in an
industrial nichrome base alloy. The high refractory properties of
this alloy are achieved on the one hand by alloying Fe-Cr-Ni solid
solution ith such high melting point elements as molybdenumPUnd
tungsten, hich increase the strength of 4he interi"E'amic-1-55as of
t'Fe -crysAaw lattice of a solid solution and slow down the process
of softening at elevated temperature and, on the other hand, by V
introducing titanium d aluminiuml;Wntensive dispersion hardening
is achieved as a result of formation of a considerable quantity of
a thermally stable inter-metallide of the hardening phase Ni (Al9Ti)
of the a-type. In addition to studying the kinetics of foKation
of the K-state in the alloy, the temperature range and the kinetics
of other phase transformations were studied. All these 8pecimens
were quenched in water after holding for 2 hours at 1200 C for the
Card 1/4
W70
S/180/60/000/005/011/033
E073/Er/-35
On the Theory of Phase Transformations in Refractory Nickel-
Chromium Base Alloys
purpose of obtaining a practically uniform solid soltition. To
establiah the temperature ranges of phase transformations, the
electric resistance was measured of the quenched specimea in the
proces3 of continuous heating and cooling by a,compensation method
using potentiometric apparatus. The K5state was very highly
pronounced (curve 3, Fig.1). Up to 450 C the electric resistance
increased continuously in accordance with the temp8rature
coefficient of the resistance; between 450 and 900 C an increase in
the eleotric resistance was observed, which is characteristic for
the K-state. To study in greater detail the k;netics of the
transformations in an alloy quenched from 1200 C, various specimens
were temBered at 100, 200, 300 400, 500, 600, 700, 800, 900, 1000
and 1050 0 for durations of O.@, 1.5, 3, 5, 10, 16@ 20@ 25, 50 and
100 hows followed by cooling in water, after which the hardness
and the electric resi8tance were measured (Fig.2),, Tempering at
100, 200, 300 and 400 C does not produge any appreciable change in
the physical properties; at 450 to 890 C the electEic resistance
increased, reaching a maximum at 600 C. Above 600 C the resistance
I
.Oard 2/4
86070
S/180/60/000/005/011/033
E073/E535
On the Theory of Phase Transformations in Refractory Nickel-
Chromium Base Alloys
decreased both as a result of destruction of the K-state and also
as a result of the beginning of the decomposition of the solid
solution. The authors also carried out experiments on the processes
taking place during a secondary quenching of nichrome base high
temperature alloys. The aim of the first series of experiments was
to qudy the speed of dissolution of the hardening a-phase at
1050 C (secondary Suenching temperatgre), Specimens which were
quen3hed from 1200 C and aged at 800 C for 16 hours were held at
1050 C for 30 min to 24 hours and then quenched in water, Following
that, the specific resistance and the hardness wege measured, Then,
the specimens were again aged for 16 hours at 800 G and the
resistance and hard-ness measured. The results, Table 2, indicate
that the hardness dogs not change appreciably as a result of the
holding time at 1050 C. Long run strength tests have shown that
the optimum 8emperature for secondary quenching of the alloy is
1000 to 1050 C; the microstructure of such specimens'shows a
relatively uniformly distributed network of relatively large
carbide particles along the grain boundaries. The best refractory
Card 3/4
W70
S/180/60/000/007)/011/033
EO?3/E535
On the Theory of Phase Transformations in Refractory Nickel-
Chromium Base Alloys
properties of nickel-chrome base alloys are obtained in the case of
the following transformations taking place successively in the
uniform solid solution after quenching from a high temperature:
rejection of the hardening grain boundaries of the carbide phase-
ageing which leads to rejection of an inter-metallide hardening
phade throughout the body of the grain and formation of a fine
sub-microscopic non-uniformity (K-state) in the basic solid solution,
The role of the K-state reduces to that of hardening to some extent
the basic solid solution by influencing mainly the slowing down of
diffusion processes in the alloy and preventingcoaCulation of the
strengthening m-phase. There are 3 figures, 2 tables and
8 references: 6 Soviet, 1 German and 1 English.
SUBMITTED: July 6, 1960
Card 4/4
S_141 4 8/60/OW/00 5/00 8/00 9
AUTHORSi VerIgina, Z.S., Livehits, B.G.
TIME - Determination of Critical Points in Commercial Titanium Alloyki
BT-3 (W-3)11@ and BT-3-1 (VT-3-1) ti
PERIODICALi Izvestlya vysshikh uchebrxykh zavedeniy, Chernaya metallurgiya,
1960, Nr 5, pp 163 - 171
TEXT: The commercial titanium alloys VT-3 and VT-3-1 (composition
given in a table) become brittle after conventional thermal treatment. To
explain the causes of such brittleness and to select the appropriate thermal
treatment for eliminating same the authors undertook to determine the upper
and lower critical points and the cooling rates ensuring the equilibrium
state at low temperatures. To determine the upper critical points the
specimens were water-cooled from various temperatures. Heating was performed
in a vertical furnace In argon atmosphere. Additionally,*X-ray analyses wnre
carried out with the use of data submitted by Yu.A,B@garyatskiy, T.V. Tagunova
and G.I. Nosova [Ref 41. To determine the lower critical points and cooling
conditions entailing the equilibrium phase state, the specimens were cooled at
Card 1/2
iU/148/60/000/005/008/009
Determination of 6itioal Points in Commercial Titanium Alloys BT-3 (VT-3)
and ET-3-1 (VT-3-1)
different rates from the P -zone (500, 200, 100, 80, 60 and 40 degrees per
hour, and the VT-3 allay at 15 degrees per hour). In alloys cooled down to
the equilibrium state, electric resistances were measured during heating and
cooling (Figure 5). It was established that the single-phase 0 -zone was
obtained for VT-3 by heating up to 1,1000C and for VT-3-1 to 1,OOOOC. The
lower critical point (probably the eutectoid one) was for VT-3 equal to
58oOc i io, and for VT-3-1 5000C t 10. The replacement of 0.75% chromium
by 1.7% molybdenum reduced the upper and lower critical points approximate-
ly by 1000C. The Annealing structure of the VT-3 alloy was obtained by a
cooling rate ot 150/hour and of VT-3-1 bythat of 400/hour.
There are: 1 tablej 4 sets of microphotos, 2 sets of graphs and 4 references,
3 of which are English and 1 Soviet.
ASSOCIATION: Moskovskiy institut stali (Moscow Steel Institute)
SUBMITTEDt November 17, 1959
Card 2/2
-17 1P, 4@
83291
S/148/60/000/007/012/015
A161/AO29
AUTHORS: Belvatskaya, I.S.; Livehits, ]@,G.
TITLE: Investigation of Secondary (Jaenc n n the Structure and
hLX Effect o
Properties of the BI617 Alloy
is
PERIODICAL: Izvestiya vysshikh uchabnykh zavedeniy. Chernaya metallur-
giyas 1960, Nr 7, PP 156-162
TEXT: .,,,The
purpese of the experiments described was the investigation of
phenome,ia,in secondary quenching of heat resistant 11314617" (E1617) alloy
'i; I.78% Al; 5.22% W; 0.26% V; 3.89% Mo; 1.38% Fe; 6.05%
(15 3% Cr; 1.99% T
B; ;.09% C, the base Ni). The alloy develops dispersion hardening at 700-
9000C, with separation of an intermetalloid phase of Ni (Al,Ti) type; the
K- state at lower temperatures remains apparently to 808-900 0C. The
standard heat tseatment of this alloy are two air quenchings (1,200 0C, 2
hours and 1,050 0, 4 hours) and subsequent 16-hours annealiRg at 800 0C
with cooling in air. It is known that quenching from 1,200 C only, with
subsequent annealing, drastically reduces the heat resistance of the alloy,
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e @anges
83291
S/148/60/000/007/012/015
A16l/AO29
Investigation of Secondary Quenching Effect on the Structure and Propertien
of the E1617 Alloy
were revealed. The lattice parameter (3-575 kX) remained unchanged. The
following conclusions were drawnt 1) The effect of secondary quenching of
the E1617 alloy apparently does not consist in formation of crystallization
centers of the intermetalloid strengthening phase only,, 2) A carbide phase
of Ni Me C type segregates on the grain boundaries duriag the second
quencRin'g. 3) The results of long-time strength tests prove that the
optimum temperature for secondary quenching of this alloy is 1,0000C Such
treatment results in the appearance of an evenly distributed chain oi
comparatively large carbide particles along the grain boundaries. 4) It
is possible that the improved alloy properties after secondary quenching
are pattly due to facilitated formation of K-state because of the transfer
of carbon from solution into carbide phase. There are 4 figures, 2 tables
e.nd 8 references: R are Soviet and 3 English.
ASSOCIATION: Moakovskiy institut stali (Moscow Steel Institute)
SUBMITTED: July 7, 1959
Ca.rd 3/3
s/14a/60/000/009/020/025
A161/AO3O
AUTHORS: Lakhman, N.G., and Livshitx, B.G.
TIiLE:. Metallographic investigation of the alfenol alloy
PERIODICALt Izvestiya vysshikh uohobnykh zavedeniy. Chernaya metallurgiya,
no. 9, 196o, 148-156
TFAXTt Information is given on the techniques and results of an
investigatic.n.of the alfenol alloy developed recently (Ref.1,3) (Abstracter's
notes The sources referred to are J. of Appl. Physics and Metal Progress).
The alloy is highly interesting as magnetically soft material; its draw -
backs are brittleness and heterogeneity of magnetic properties even in a
single heat. The ii4vestigation purpose was to find out the effect of the V
cooling rate in crystallization and of homogenization of oast metal. The
investigation presente a part of' work on melting and working alfenol that
has been done at the Institut prptsizionnykh splavov TsNIIChM (Institute of
Precision Alloys of TsNIIChM); the metallographio investigation has been
done by the Moscow Steel Institute. The alloy has been melted Zrom armoo
iron and4-5OOO (A'7000) aluminum, with 16-3% Al and below 0.02% C, in an
Card 1/6
ON
S/148/60/000/009/020/025
Metallographic investigation,,. A16l/AO30
open induction furnace, with the use of boric lime ("borkallk") and oryolite
slag. The-cooling rate was varied by teeming into water-cooled copper ingot
molds, steel, and ceramic ingot molds, in 2.5-4 kg ingots. Cast metal was
homogenized at 1100 and 9800C. then forged. and rolled hot and warm (6000c)
into 0.35 mm thick strip. The investigation consisted in chemical analysis,
macroscopic and microscopic analysis with quantitative metaliography methods
and an electronic microscope; hardness (Rockwell), microhardness,. micro-
thermo-e.m.f. and electric resistance were measured. Segregation of alumi-
num was very high (2-4%, and even 6% in one in'got);,hardness varied between
Bland 13-5 :IB in one ingot. The alloy'proved extraordinarily sensitive to
cooling conditions; the worst porosity, deepest Shrinkage holes and hetero-
geneity of grain was obtained in ceramic molds. Best results were obtained
-in water-cooled copper molds, but with high stresses that caused deeper
cracks and folds in rolled strip. Homogenization in 11000C fbr*46 hrs
drastically increased grain size, with smaller grain in the ingot bottom,.
and fine grain around the shrinkage hole (apparentiy due to impurities);
homogenization in 980' increased grain size only slightly, slightly affected
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Metallographic investigation ... A16l/AO30
hardness and reduced electric resistance,, Cast, homogenized and forged
alloy had a peculiar network of parallel intercrossing lines in macrosectiora
visible even with the naked eye (Fig.3,a). The network was not present on
the ground surface. After deep etching, regrinding and repeated etching,
the metal crumbled in triangular and rectangular pieces. Several different
network tyres were stated (Fig-3, apb,c,d ). The nature of the network
has vet to be studied. The microscopic structure contained different
phases. CAbstracter's note: The description of crystalline structure is
given with.. references to 10 English and German language sources/. it is
said that the nature of the revealed phases needs further study. The pre-
sence of Fe-Al carbide and aluminum nitride is supposed, and it is concluded
that alferiol melted In open furnace must be considered belonging to ternary
Fe - Al- C, or to quaternary Fe - Al - C - N system. It is stressed that
the presence of large carbides and nitrides on the boundaries and within
grains may cause brittleness and probably causes anomalous grain growth at
high temperatures. N.P.Gromov, Y.A.Gratsianov, A.A.Gerasimenko, B.V.Molo-
tilov and V.A.Fedorov of the Institute of Precision Alloys carried out the
investigation at the institute. Graduate of the Chair of Metallography
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Metallographic investigation ... A161/AO3O
17 Ye.M.Strug carried out the microthermo-eom.f. measurements. There are 4
figures and 17 references; 3 Soviet-.bloc and 14 non-Soviet-bloc.
ASSOCIATION: Moskovskiy institut stali (Moscow Steel Institute)
SUBMITTED: 16 April 196o
20254
1. gt) ri S-4 1 OLI SI-4 60/000/011/011/0115
A46' IYAOXIO
AUTHORS: Zakhtirov, Ye. K.9 Livshits, B. G.
TITLE- Investigation of traneformations in the cobalt-chromium-
-titanium system
PERIODM@Lt Izvestiya vy,,3hikh uch6tnykh -aved.@,niy. Chernaya metallurgiya
I I
no. Ili 11960, 05 - 12
TEXT: The work is tho continiiation of a f,,tlidy of the Co-Cr-Ti @-.qui-
librium diagram; solid jtaAE cqui.librlurr, data dcterm.1nded at 1050, 950 and
7rO0C (R(jf@ 'R r 1@4-Q@j14n, Yn 1), Khrrfn. Zhurnul noorganicheskoy
khimil, 1'. 3, no@ 3, 1956; Ref. 2: Pt, 1, Kripyrtkcivich, Ya. D. Khorin.
Nauchnyy(, doklady yyashc-y ahkrly, Mnutll.iirgiya, 1,95s, 110,I) had to be com-
plemented. The piatint@m-platinorh:,,dium th-@rmorc,.,-plfl in an alAminilm oxide
hood uae6. in this experiment aerJc-3 hael a hIgh degree. of accuracy. The
allotropi.- transformat-ion *ao Jnvriatigatod by rlllatomr-iri,@ and magnetic.
methodo; the Curis., pointa wcr,i dptcrmin.@.d at thf? samn tiic.@-. Tho cobalt
alloyo under aVid.y containtA. lip t@;. 601,'@,, Cr and up ts 35 @6 Ti. The experi-
v_,ent xnro@.lts are shown :Ln tiv, d1lagram. (Figure. I,) tha-@ includes a new phase,
C;ard 1/5
20254
S/14S/60/000/0!'/01!/015
Irvestigation of transformation in AI@I/A030
S , revealed beyond the Ti solubility limit in alpha and beta Co. This
intprmetallic compound se6mad to have a structui,t, resembling the Ili Ti
compound described in (Ref '601 F. Laves, H. J, Wwlltaum. ZBchr. f Kr@s tail 0-
graphie. v.101,, 1939, P@ 78, and Ref. lit A., Taylorg 11@ W. Floyd. Acts,
criBtallographica; 1950, 3,, No- 4, p. 285) and CO M,, and C-3-AW found by M. M.
3,- j
Babich, Ye. N. Kis.1yakova and Ya. S. Uman5kiy in ;938 (Ref_. 12: ZhTF, 1938
No. 2. v@ 6). A ternary intermetall-12 compound waa revealed also in the
teTnax@- systemi C04Cr2Ti (or.( -phase) (Rof. 4, ), and 1 1. had to be. determined
If It was a stable chemical compound or jict. The information includes the
diagrams prepared in experimento anl A dotalle-d dis..-assion. of objervations.
The -.4 -3hase proved uns table and was formed by priritptir reaction in 1150 -
- 1200 . The two-phase state revealed 0, th.? (-' nd of Crystallization sepa-
rated into two three-phase [i + A f,!, E + (Co, Or)2Tj1 and two two-phase
states [IJ + @j E + (Co) C r) Til .The stated cffect of 6' and T1 on the
temperature of magnetic (93 F*,-nd allotropit: (A, ana Ar) tran.9fnrmation3 is
shown in four graphs (Figure 4)., Alljy.3 ajlj.-@Jnlng the Co--TJ Bide of the
composition triangle in Co - @ intfrval and e@ont;-,inlnG 15 - 20 4b Or include
a eiomponent analogous with the binary Wj th a
higher Or content in ternary @illoya, no de-ompositi-on wz-t-q observed; Cr
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Investigation of transformation in ... A161/AO30
additions r4ised theck-Co;@@,'J-Co transformation temperature. The allotro-
pie 6---) 6 transformation observed in Co-Cr alloys in 1310 - 126oO (45 - 5L9 OP
Cr) -mao.observed in ternary alloys as well. The thermic stop in 12aO -. '
- 12700 stated in alloyo 60 1j'v Cr - C02Ti and 55 @'. Cr - C02Ti at addition
of 6 % Ti corresponds with the allotropic transition. Magnetic trans-
formation occuxred both above and below the Ac point, i.e., in the alpha and
in the beta phase. This indicates that solid state equilibrium is diffi-
cult to reach in temperatures below 6000. There are 4 figures and 13 re-
ference3: 6 Soviet and 7 non-Soviet bloc. Two English language @ublicatiom
read as followb: (Ref. 8) A. rlsea, A. Westermann, G. Manning, Metalo Tech-
nology, 15, ITO. 4, 1948, 13 - 24; (Ref. 11) A. Taylor, R. W. Floyd, Acts.
cristallographica, 1950, 3, 110. 4, p. 285-
ASSOCIATION: Moskovskiy institut stali (Moscow Steel institute)
SUBMITTED: March 29, 196o.
Card 3/5
rs
82643
&
R@! S/126/60/010/02/014/020
E111/E352
AUTHOR: Livshital B,G.
TITLE: Solid-solution Heterogeneity and the Initial Stage of
Ageing in Iron Alloy A
PERIODICAL: -Fizlka metallov i metallovedeniye, 1960, Vol. 10,
No. 2, pp. 272 - 284
TEXT: The author deals with the K-state (so called by Thomas,
Ref. 1) of' single-phase alloys. This is characterized by changes
in many properties (Refs. 1-5). -The author presents data showing
that the same considerations apply to iron-nickel alloy (365,0* Ni)
containing 5.5% niobium. He shows the electrical resistivitMf
this alloy as functions of tempering temperature (300 - 65o
for 1-50 hours' holding time (Fig. 1); all the curves show a
maximum, the resistivity also rises with increasing holding time
but this effect decreases with rising temperature. Dilatometric
and microhardness measurements confirmed the resistivity indi-
cations of the K-state. Th 'e beha4our of the alloy suggested anal-
ogy with the two stages of ageing in aluminium alloy. To check
this the author, in collaboration with Van Zhun', studied the
agein6 of the alloy and type N36KhT alloy, after hardening from
1150 C in water. Fig. 2 shows the resistivity, Fig. 3 the
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Solid-solution Heterogeneity and
Iron Alloys
289N
S/1 0/010/02/014/020
E111/E352
the Initial Stage of Ageing in
saturation magnetization and Fig.04 the hardness as functions of
tempering temperature (100.- 900 C) for tempering times of
0.5 - 7 hours; two stages of ageing are evident in each figure.
In the high-temperature stage precipitation of second phase was
detected metallographically. No evidence of second phase was
found for the low-temperature (up to 600 OC) stage. The low- and
high-temperature stages involve opposite changes in saturation
magnetization. X-ray diffraction analysis shows that the small
decrease in lattice spacing at 300 - 90 0C is due to K-state
formation; the increase at 450 - 6oo C corresponds to �ts
elimination; that at 600 - 800 OC indicates a sudden change in
solid-solution concentration through precipitation of second ph-ase.
The author estimates the activation energies for the low- and high-
temperature ageing processes at 40 000 cal/g atom and 71 000 cal/g
atom. Reversion after ageing was studied at 350 - 600 oc,
followed by 5 seconds in mciten tin at 700 OC. Fig. 5 shows
resistivity, saturation magnetization and hardness as functions of
time for the various parts of the heat treatment. The investigation
Card 2/4
82643
S/126/6o/oWo2/oWo2o
Solid-solution Heterogeneity andERI/fARial Stage of Ageing
in Iron Alloys
showed that K-state formation and precipitation of the second
phase develop independently and can, at certain temperatures,
proceed together; complete reversion is only possible before
the new phase precipitates. The author notes that similar
effects were obtained for N36KhT alloy (Ref 9) and describes
experiments with this alloy (34.5% Ni, 12.43% Cr, 3.62510' Ti.
remainder Fe). Figb 6 shows resistivity as functions of temp-
erature (300 - 800 C) for varlous ageing times (0-5 - 6 hrs).
To elucidate the nature of the low-temperature stage the
influence of cold deformation on the properties of low-
temperature aged alloys was studied; Fig. 7 shows resistivity
and hardness as functions of deformation. It appears that in
this alloy, the K-state is produced by tempering below 500 oc
and destroyed by deformation. Incomplete restoration of th a
alloy properties occurred gfter ageing at 400, 450 and 500 C,
with brief heating to 700 C; Fig. 8 gives the resistivity
and hardness as functioigs of ageing time at 450 OC (n.b. given
as 500 0C in text, 450 C in figure caption). Similar results
Card 3/4
Solid-solution Heterogeneity
in Iron Alloys
62643
S/12@/60/010/02/014/020
Elll/E352
and the Initial Stage of Ageing
were obtained dilatometrically (Fig. 9 gives length.-change
as functions of time for various isothermal holding
temperatures). The author also reports experiments with
Fe.-Mo (21 and 13% Mo) and Fe-W (16 and 9% W). Results
(magnetization and coercive force, resistivity and hardness)
for the 21% Mo alloy are shown in Fig. 10 as functions of
tempering temperature. He gives results for some further
alloys (compositions in Tables 1-2). The general conclusion
of the author is that the K-state is analogous to the
structural state of a supersaturated solution with Guinier-
Preston zones, that such zones can occur in unsaturated
solutions and that they do not act as nuclei for precipitating
phases. There are 10 figures, 2 tables and 18 references:
9 Soviet, 4 English, 4 German and I Japanese (in gnglish).
ASSOCIATION: Moskovskiy institut stali im. I.V. Stalina
(MOSCOW Institute of Steel im. I.V. Stalin)
SUBMITTAD.- February 6, 196o
Car@
I)Lil
1004
S/14 61/000/ 6/010/015
. -Z
Ail 61YAi,3
AUTHORSt Li-shits,___;@. G., and Rymashevskiy, G. A.
TITLEx Characteristic temperature of Ni,,Fp + niolybdenum alloys
PERIODICAL: Izvestiya vysshikh uchebnykh zavedeniy. Chernaya metallurgiya,
no. 1, 1961@ 151 - 157
TEXTt The Moscow Steel ln3titute conducted the subject investigation
in view of diffv@rent opinions in literature on the nature of transformations
Jn permalloys alloyed wt-rh more than Mo. The composition of the studied
alloys is given in the table (in weight of Qomponents):
.Composition no@ Mo Fe Ili C 11C, L-12-210
I Traces 76-;Q 0.032
2 1.2 @1 76-U 0.032 0.73
3 3.2 76.6 0.636 11.96
4 5.2 76.o 010,56 3.22
5 7.2 -.16.d 0.023 4.49
6 10.2 76@0 0.023 6.45
Card 1/8
'Ili @ il
Characteristic temperature of ...
S/14 '61/000/001/010/0!;z
A161YA!33
The alloys were smelted in a 10,-kg capacity induc,'ioi., furnace, hot forged
and drawn into 5 mm diameter specimens. Specific electric resistance, Young
modulus, modulus of shear, and. the charaoterlstical Debye temperature were
measured. The elasticity modulus and Debye temperature we.re determined by
measuring the natural frequency cf longitudinal and torsional oscillations
of specimens gripped. in the centar and subjected. either to alternating com-
'pression or to alternating torque by tranqmitters of corresponding design
described. by V. I. Kf@rotkov TRef. 9% CM v M '%FIM i M) v. II, no. I , 1956- -
The Young modulus (E) and ab@ar modulus (0) aer .e calculated by the form.ulae
41, 2 2
E = LI kgI..2-
58-1 '. @5
4L2 f2
G = . t kg/mm2 (2)
981.1o5
where L is the speci:,en length; density; f, - natural frequency of
longitudinal osaillationa; ft - natural frequency of torsional oscillationi
The elasticity modulus was determined with about 0.47-' accuracy. The char-
Card 2/8
S114816-,1000100110101015
@.Characteristic temperature of... A161/A133
acteristical :Debye temperature'was also calculated from the natural frequen-
of longitudinal and torsional oscillations, by a method suggested by
N4 Finkel.'shteyn and V. I. Korotkov (Rof. 10: DAN SSSR, no. 5, v. 108
1956@ 846)@ The formulaJor calculating.the characteristioal temperature
3T
3
A W
'A
-j;-
k,
4-
and the accuracy of 0 determination is about 0.4%. All alloys were brought
into an initially disordered state by quenching at 1,0000C in a.10-1j4 aqueow
Then the quenched alloys were tempered at 3800
solution of FaCl. with 20 to
620-min soaking. The compound states were fixed by.quenching in water. All.
properties were measured at room temperature. Measurements were also made
on alloys in the cold-deformea state, with about 4T/.' deformation, 'for com-
-parison. All. alloys were monophase solid sclutions, The investigation re
sults are given in graphs. Ls can be seen (Fig. 1) the Young modulus (E)
Card: 3/8
24al
S/148/61/000/901/")10/015
@Characteristic temperature of... A16i/A133
and shear modulus (G) changed in an opposite sense, G slightly dropped, and
E alowly increabed. The increase of the Youn,- modulus became considerable
at high Mo contents. The Young modulus and characteristical temperature
change were also opposite: 9,docreased with anincreasing 11o content
from 450.K fo:r N'3Fe to 4430K.for alloys with VY16 Mo in,the quenched state.
This difference was higher after temperingt 45901C for N13pe and 4460K for
alloy with 101,ro Ito. The electric resistance varied as shown in (Fig. 4),
and the Young-modulus, shear modulus and characteristical temperature as in
(Fig. 5). The electric resistance behavior indicates the existence of two
Processes in 1"3Pe + Mo alloy that are leading to opposite variations of
resistance, and the same is apparent in (Fig. 5). An addition of Mo to bi-
nary alloys results in a drop of the adhesion power at the beginning due to
the disordering effect of Mo, but this process is reversed-beginn-iiig with
114a Mo. Ordering seems to start with the formation of a new ordering phase
which increases with tempering. As the ordering process in*N'3F@ causes a
::.reduction of VDlume, and the atomic diam4ter of Mo is 12% larser than of Ni,
it may be supposed that Mo atoms are getting displaced t6 the outside of the
antiphase domains, segregate there and limit the spread of domains. Thus,
Card 4/8._
)4@
3/14 61/000/001/010/015
Characteristio tomperatu.-e of... Al 61%133
the two diffe::ent procesees in Wi Pe+Mo diiring tempering are apparently the
3 V
ordering and -the segregation of..Mo-atoms (K-state). The maximum in all
curves indicates that ordering takes placp..in Ni-Fe-Mo alloys at any Mo con-
tent. A comparison of data with the data obtained by A. Z. Ivanushkina
-(her dissertation for the degree of Candidate of Technical Sciences,, Moscow
Steel Institute, who studied the effect of the Mo-content on the
1956)
electric resistaice in Invar, but it seems that the much weaker effect 'of
Ho in this case can be explained by the many tines weaker ordering process
in invar. There are 6 figures and 10 references: 5 Soviet-bloc and 5 non-
Soviet-bloc. Two references to English-language publications read as fol-
lows: I. Nix, L. Beyer, B. Danning. Phys. Rev., 58, 1031, 1940; R. M.
Boothby, R. Bosorth, J. Appl. Phys.,-.18, 173, 1947.
ASSOCIATION: Moskovskiy institut stali (Moscow Steel Institute)
SUBMITTEDt March 2,'1960
Card-5/6
124 21L
S /11 46 iooo/o o 0 15/0 1
A , 6
AUTHORS z Ver.1gina, Z, S., and Liv--h.ite, B.
TTTLEP Dr-terminlng the mechanical propertLes of the &T-3 (VT-3) rn4
PERIODICAL: lz-iestiya rpaehikh -,ic.br.-bnykh zavedeniy,, Chernays metallurgiya,
no. , ":1@6!, 170 .. 17--
TMT x Twr; industrial heat2 of 3r-3 @VT.,', ar.' e@ 3,-! alloys have been
Thei.r ohemloal composition @i a
@x
A1 Mo 02 N 2 S1 Fe H2 c
VT-5 Baile A-87 ? P6 - - 0.20 0,16A, 0.04 0 -12 70@00@ 0.03
VT,.;-.] BaS e 4.-1 2 ! 1, -
-,4 1.7 0.2 O@053 9,14 0@27 0.003 0,05?
The invest.i,gation pitrpoe-@ waa@, '.% TQ' determine the clecharroal properties
A
(in tension. and Impa-@t testO,aft-or,anneal.ing to practically full equilib-
.1-T. :3tato; 2) Tn jr.Ti1oY;:!t rate that tile irpvhani(.a!. proper-es are, n,,t Chang-
,ng dur-ing hc@a!.ivg to *114:- tempermure -.f Lhr- specLmeriF, had bpen
to st;xl,r-; Tc ehrw 0,at the starda:d indu2trial beat
Oard 1/1
0
S 14 6 1 00 00. /013/0
,Determining- the mechanical pro;erz.,es o," A ! 3
treatmE.nr rules result i.n a resid-.ial euparr.A@oled C" 1:@hase, and that the al-
loy onrAtaining residual h_'gh-temperature r- tecomes bxittle ;ri h,@a?-Ing, i.e.
that tbe impacf reiilstari,@-7 -is lowered@ Tne standard, h4:at t.-r7.,itment spe-@;ifi-
cation h@raling at 8700C, ;ool;rjv, in the. ffurria-_t, It:-wn Io. 650' and
boaking for I hotir at th,@-: temperature, ths@n in oper, air. The ar.-
?.,Ir.le inrludes two ta@li-s gi@,Ing th- rropezrtif-s tourid in boi@h al--
loys ir. tbz_, t6f t,@ aft-vr tbe standard hpa,: treatmont , anj af ter arxz,@ailrr, *.o
L--ib-.: s !-q*,.e that h@id beer; so annealed hari tha
strength r,@-quir,?d b.'j, ?-I-,e @@tandsrd and their ;mpa@@t resis@--
ance corresponded f @ the- upper a I arviard ri@qul rement 1 imi t. @ Thu@!, allo.ys all..
ncalpd to practical equli.brlum @ad good strclngth and' high impact resistanre
desp-lte the very slow cooltng used in the experi-m-ent.- (40 and 150/hr). Th is
Ls supposed to be due @o impiirltiee (02, N2) diesv-1-d in annealing at hAgh
temperature (in fs-range) and then retained in c4, dospite very slow cooling.
Specific electric resistance increasEd at higher harderii-rig temperatures ir
the A-range, but hardness rose oniy slightly. At. 11,,@:her h,@ating for harden-
.ing, the Jmpuri.ties (02, N2) dissolve in the r-phaue ` and thry are alloying
elements. Higher-alloyed. A yields martensite with h@gher electric resist-
Card 2/4
2h 214
S 48 /6 1 /000/00: /0 13 /0
@Determiaing the mechanical propertlr-@@ of A1,61A.13
ance and higher hardness, but the hardness is compensated ty a higher quan,
tity of residual soft P, and this accounts for only a slight increase ir,
hardness comparing to the increase in electric resistance. A special in-
vestigatlon is necessary to study the kinetics of M-artenaite decompositien
and transformat@on of residualSduring tempering, but it is apparent that
alloying elezent6 are better u ized at higher heating temperature for
hardening and. annealing. It le pointed. out that tensile test specimens an.
nealed as prescribed by standard heat treatment specification dpvoi.,.)P@-d a
cl-r-arly expreBsed. nPoV., and they ellnngated. mainly on account of the nen@-.
ipE(A-m,?ns a.
artealed tc pre.t.,t.tcall equilibrium stretched over nearly thAFAr t1r.-
length, wtlhout anf ntck. It. had been zt.ated by the au@hors prev'o-ju!?] 'y
`7-f% 1, U-.sh:ite and Veri.gi'na, Izv. vyssh. uch. zav. Chernaya metailurglya,
no, 5@ 1960) that, 1-he srod:rt-d alloys i.n thri equilibr,tm state consis* uf ar,
.-.Vjhas(? and TiCr?, and aft-cr anneaxiing a.-@ @Pr standard. appeif teat .;,@ne tkir-Y
a residual (S-.pha,-,;,, AP tho quantity :@f Rl-1p planee' in th@- hexagnpsi`k
,,4- phase latt-,'ce .1o smaller than in the rutic tody----@nti-T'F@d ('-phasc, 1hp rJf,.
foymatJon of to?nBion tf:lsl iqjtn,,imen- (JiM-rent. S-pecirrons anncaied to
practical. equtibyium d,-p ti,-,t bok-(:mr! trittlo, wh-',tt h@-,ated !Q temperatures bri.
low the r:ufr,,1Uc-. The lowor t-)undary of the eute-tir ranl5F' for VT 3-1 alloy
Card 3/4
242 11.
tl
3'.*46/6-11"000/00 1 /013/015
Determining the meohanLCal j)rQFer,LPS Of- A,WAI-33
is at 500j!01C, In annealing av per standard eper;if'Acation the impa3t rol-
sistance of speoimeno- dropH after soaking In 400, 4@O, 500 and 5500. Con-
clusioas; 1) Annealing t:,i prnorloal equilibri.um state yielde a strength
within the standard requirements and a high itrpact resistanoe. 2) The
mechanical prt3perzies of thi) alloye after annealing to equilibrium do not
chan.ge after tieating to r-utertic, temperature. Thus, the Working tomperature
of the alloys oan be raLged. by produe4ng alloys with higher eut:Aotic temper-
ature. 3) Annealing as required In Standard apecifisaillons raises .1trAngth
to the upper 1.1m-,t (of standard xequlroment range) and yielde b1gh iinpact
resistanoel aftey- heating to 400 -- 5500 the iippar.--t resistance dropp.. Em-
brittlement 113 apparontly caumi4d by the formation of the martenatte phaseg
dljrJ.ng the dooompasit!on of the rpoidual P-phaae, There are 3 figuroo, 2
tables, and I Soviet-bloo reforence.
ASSUCIATIONa Idookovskly institut stali (Moscow steel Institute)
SUBMITTEDs June 21, 1960
Card 4/4
27241
S/148/61/000/003/013/015
j A161/A133
AUTHORS: Livshits, B. G., Rymashevskiy, G. A.
TIM: Variation of the bond forces of solid solutions in the,NI - Co - V
system
I
PMODICAL: Izvestiya vvashikh uchebnykh zavedenly. Chernaya metallurgiya, no.
3,'1961, 154.- 16o
TEOM Detailed information is given on the techniques and data,of an in-
vestigation conducted for the purpose of contributing additional facts necessary
to obtain high-strength alloys. The characteristical temperature (9) of the alloys
was determined by Variations or the elastioity modulus, and an as mbly was con-
structeii to'determine,the Young Is modulus @E) and the'roodulus of lasticity in
shear (0) tT the method of Ostroumov and F4rotkov (Ref. 3,4: B. Ostroumov and L.
Polotovskiy, Vestnik m:etallopromyshlennosti, 1933, 5, 1.4; V. 1. Korotkov, Fizika
metallov i metallovedeniye, t. II, VYP. 1, 1955). The electric resistance, hard-
ness, density, the Curie point (T ) (by the Akulov anisometer) were measured.
C
The metil properties were studied on specimens after annealing at 1,2000C with 2 h
holding,, and aftex .@ quenching.from 1,2000C with 2 h holding. Bindry Ni-V and ter-
nary'Ni-Co' + V aliays were melted in argon in a high-frequency furnace and poured
Card IA
21241
1 8/148/61/000/003/013/015
Variation of the bond forces of solid solutions ... A161/A133
in argon In-to a copper ingot mold producing 600 800 g ing6ts. The composition
of the stuctLed alloys was the following:
I I I
No. V dig
(weight) Co, %
(weight) Ni, %
(weight) No. V, %
(weight) Co,
(weight)
4-- Nil %
(weight)
1 0.131 Traces* .6 o.9 49.81 49.29
2 1.91 7 2.21 49.91 47.88
3 3.75 8 3.86 48-31 47-83
4 8.33- 9 8,55' 46.19 45.26
5. 11 -47 10 51.0 51.0
The article tacludes.-the formulae used for t@e determination of R, G and 0, and
references to obtained dsta by Broom and Barret (Ref. 6: Acts. Mdtallurgica, 1953,
V. 1, no. 1, MY,*P 305) and k8ster (Ref. 7: W . Khter, F. Spazzmer, Z.f. Metall-
kunde, 48, no. lo, 1957.). Phenomena Were observed.as listed in the following.
The property curves of Ni-V in the quenched and annealed state, and Ni - Co - V
Card 2A-
27241
B/148/61/000/003/013/015
Varia@ioh of the'bond forces of solid solutions... A161/A133
in the,quenahod state show monotonous variation with a changing composition; E and
G,and eleptrio resistance are growing with a raising V content. The resitance
curve; of Ni - V alloys has a bend at the Curie point, and of Ni-Co-V a maximum - it
had a highet electric resistance when cooled to room temperature. A peculiarvari-
ation of the.elastioity modulus and Poisson factor is seen in annealed Ni-Co-V
alloys.. Gene;-allyit is obvious that. the properties of the Ni-Co alloy are chang-
ing as this would be expected in an. brdering'al-loy. Addition of a third element
with a large atomic radius to a binary ordering alloy, i.e Ni Fe + Mo is known
-1" @eous soiid solution
to replace the ordering process by a peculiar state of heteroge
("K-state"), and same was seen in Ni-Co-11 alloys. An addition of only 1% (attomia)
V.to'Ni-Co inverted the "nse of the sffeat on electric resistance. At 2.5% (at) V
the resistance of the ann4aled alloy was higher ttum that of the hardened. Further
raise of V content slightly reduced the resistance increase rate in annealing. In
other words,lalloys with abo4fe 1% (atomic) V hsA tha K-state. An increased V cont-
ent in Ni-Co-V alloys also caused an Jmorease of the Young's modulus'in the anneal-
ed state gompared with the hardened one; a maximum E increase was stated at 2.54%
(atomic) V content, and reached 13%; an increasing V content in Ni-Co-V alloys -,-e-
ducdd',the modulus of the elastic-ity in shear in the annealed stated compared with
the hardened one, the.maxinrilm effeat. was observed in an alloy with 2.54% (atomic) V
VN@
Card 3/4
Variation of -,;he'bond forees of solid a-Autiona ...
27241
3/148/61/000/003/013/015
A16l/AI33
and reaohed 6%. The characterist:@i -temperature Increases during the ordering of tbe
binary Ni-Co alloy, and an additicn of V to the binary alloy reduces the bond forces
increase. At. 4.4 and 9.7% (atomls) 7 the characteristic temperature is practically
same in hardened and annealed alloys. The Polseson factor practically does not
ahange during Vie ordering of NI-Co birar7 alloys, but grows when V is added, and
reaches'the maxiimlm at 2'.,R4% (atomie) v, L.e., In an alloy in which the electriu
resistance, thn Young% modulus and elastioity modulus in shear attain also the
maxiiwam value. There are 4 filg=-ez and il ref4brences: 8 Soviet-bloc, and 3 non-
Soviet-bloc. The t"Oro reterences to English-lanVaage publications read as follows:
T. Broom and C. S. Barret. Acta Metallurgica, v. 1, no. 3, MAY, P; 305; N. W.
Lord. Journ. Cnem. @hys., 21, 692, 1953.
ASSOCINTIONt MoskGvakiy inst-11-I.-Ut atali-(Moscow Steel Institute)
SUBMITTO.- November 4, 19,1-9
card 4/4
AUTHORS-
TITLE-
2886
s/AoAl/ooo o
Ell]/E7,80 &Voo6/020
B'71 j y -a N,-.: v- B.13. -@nd Potalk, Yq.M.
(M 0 S C v -,v )
The --4- a z - t ,n !Ft i. f- (.- C r a r, -:3 f o r -
a t oil
PERIODICAL: 5SSR.. I y a Otdeleniye
t ki-ill all@lj-.; j -,a L toplivo.
4 ,
TEXT. T I.ta-f erri! Lo a-Lniess steels
1-1 ",1- , J. 13 C.! i C a ri f, effect vn the martensite
-L-@-- @uwards higher t emp eratur es
.1 1: . J . I . Llewellyn, F.P. Pi@z;kering - J. Iron
and SLe;.,,! Yn.-A 1.92 , No - 3 (Pr ub 1, ewy sovremennoy
tclt, in other, in,4tajices, the effect
li abseitt'. V!%.- aimed elucidating this
P-vcblem. thi:,k:ov beats were usedj nach heat was
t e ei-.ri ed J t! 5, J. 0 . Xudividual bat(,1ie?s dAffered in the
C-obalt or f,4 l.-iu;i -L r, rv@ 0 n t ull t- . The delta ferrtte was isolated
fx-cm one heat (r,.05(1*.,J.', C, 0.58 Mn, 0,28 SL, u'14.50 Cr, 7.60 Ni,
Card 1/3
231868
s/18o/6i/ooo/004/006/020
The role of delta-ferrite EIll/W380
0.14-1.90 Al in the different batches) by anodic solution
in an electrolyte containing 350 g/litre FeCl 3 and 20 ml,/litre
of HCl tk0z-tractorls -note - the text gives 1120 mm/litrej. The
delta-ferrite was subjec.Ted to microcbemical analysis. Since
martensite and carbides were absent after quenching from 1 050 'C,
the austenite composition could be calculated. The influence of
delta-ferrite on the marten.91te transformation uras studied on
two other heats, urhose rornposition (respec_tk@,-ely, 0.06, 0.090,10 C;
0.53, 0.54 Mn; 0.28, 0.42 Si; 16.88, 3.15.20 Cr; 2.69, 4.60 Ni-
0-11.3.2, 0 Co; 0, AI) was chosen so as to give inartensite
points abov-e room temperat ure in each batch. Various quenching
temperatures werr- iu@@ed alid the effect of aluininiut-ii, cobalt and
delt.a-pha-,e cifi -.1'.-ctensite tra_-i-sfc@jrination was studied.
Thr- authri-f-r; di@lta-ferrite iFq)p@-,aring in the
6-tructure of F,-, Produces a substantial redistri-,
bution ov Aod Ving eloments bct,,e_@n delta-ferrite
and austei-jite, I.E.I,.LdIng to a drop in marten.:s.if.e-transf ormat ion
temperature, t@.,e drop 1.,Icreasing with increa.-@ing delta-ferrite
Card 2/3
28868
S/18o/63./ooo/oo4/oo6/020
The role of zill/E""90
t. 1@ it, a ab s enc. e cj r
content. TI)e
carblde@@,, small q;-@z- lead (-Atijer (.,.) i
t,-mperatctro (it- to
;1 i gb t 7-_ r eas,@@ j frli 1.7 F_- I
decrease, smalley, 'y I r- I I el'! In (111 t a r I? o ed E d
to elucidrAt e tbi -4 -A V1 t a 1: L t e I i-- a di t o a c j I s i d ey a bl e
increasi- in beating tliat results
in carbide lorint-0 more ii3tensive
s epa. I-at i 0 11 o f t 1-1 C- is a r e -1 1-a f er r- i t, e/aus t en i t e
boundarl es c.omp,_- r ;"@ i litt.i ", "Wau.s t ertite boundari es.
Th e r e a r R 2 f - i, -@md 71 r @" (!rit @ z " 2 Soviet-bloc
a.nd 5 no 11 o VJ. v i, I "i r 16 k e_- @. 2-11 V. I L!i h - I a n Lm a g e
r ef er ew@ 0& @5 quo t. I - q(10 t k,rj i -1 Ref. 2 -
F.C. Monkman, F.E',, N' .% Gj.-;.:int Metal Progr., 1957,
v- 71, no. 4; P Sl- irl ey 1, on and St eel Inst . ,
1957, .174. ;,-. 7 P H. C. Vo@lt et , C - J . Bechtoldt
J. Res Na t.. B,j .1 -454 , v. 3 2.
SUBMITT ED. F e L) a)- y 2 1,
Card 3/3
AUTHORS: Belyakov, L.N.
TITLE: Delta ferrite
PERIODICALs Akademiya nauk
tekhnicheakikh
1961, 90-95
S/180/61/000/005/014/018
E071/E435
and Livshital B.G. (Moscow)
in an austenite-ferrite stainless steel
SSSR. Izvestiya. Otdeleniye
nauk. Metallurgiya i toplivo, no.5,
TEXT: The influence of hot plastic deformation (forging and
rolling) the retention time at temperatures of homogenization
(1050 to 1300*0 and cooling velocity of ingots on the amount of
6-ferrite in an austenite-ferrite stainless steel (C 0.07 to 0.09;
Mn 0-44 to 0.70; Si. 0.52 to 0.70; Cr 14.53 to 15.73;
Ni 7.7 to 8.8; Mo 1.60 to 2.30; Al 1.30 to 1.38) were
investigated. The determination of 6-ferrite was done.in all
cases by the metallographic method with an accuracy of + 0.5 abs.%
and by the magnetic method'with a relative accuracy of + 3%.
For the latter method, specimens were austenized at 105ec for
15 minutes, cooled in air to 300- 250*C and annealed at 2500C for
1 hour in order to stabilize the austenite, It wits found that
the velocity of cooli.kg of.the ingots has an influtince on the
amount of 6-ferrite i the austenite-ferrite steel,, The lower
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Delta ferrite in an austenite- E071/E435
the cooling rate in the range of crystallization temperatures, the
higher is the content of 6-ferrite in the cast steel. In the
axial part of the ingots weighing 25 and 450 kg the amount of
6-ferrite is 1.35 times higher than on the periphery. On the
periphery of the ingots, martensits is present in a considerably
smaller amount than in the axial part. Hot plastle deformation
of stainless steel at 1000 to 1100% lowers substantially the
amount of 6-ferrite, whereupon forgitig and rolling preduce
equivalent results. A non-uniform distribution of martensite-is
more stable, but this non-uniformity of the structure is removed
on rolling a 450 kg ingot into plateli 6 to 2.3 mm thick, On
heating cast and forged steel to 1050 to 1150*C and retaining it
at this temperature for 0.5 to 5 hours, the amount of 6-ferrite
changes only a little, whilst at 1200 to 13000C, it inareases
substantially. Hot plastic deformation at 1000 to 11000C lowers
the amount of 6-ferrite considerably faster than annealing at the
same temperature. It is considered that the non-uniformity of the
distribution of 6-ferrite and martensite in ingots is due to
dendritic segregation, since zonal non-uniformity along the cross-
section of an ingot is insignificant. There are 5 figures,
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AUTHORS Livshits
T ITLE Stijdv of
nir-hrome
: -^- 3 9 951.
S/148/61/000/005/009/()15
Elll/Ei8o
13,G., Rymashevskiy, G.A., and Kosyreva, NIP.
bonding forces in alloys of the
type
IV.!i1ODICAL: Izvestiva vysshikh uchebnykh zavedeniy.,
Chernaya metallurgiva, 1961, No.5, PP,, 139-L46
TEXTz It has been shown that some alloys with a sing;IP-phase
salid-solution st.-uctu:e ba!ied on transit ion-Sroup metals show &n
anomalo-us changF@: i-r resistivity diirinfgr tempering; after
hardening or cold deformation The signtfican:!P. --f thp K-state in
alLoy properties ha!; been in!,,estigated Ref.,6i, Sh.Sh, lbragi-
mov, B,G. Livshits, FM i M V,4.. 1957, No@2, 315), and orderjniz
effects were considered by Yu A. Bagaryatskiy and Yi,l)- Tyapkin
(Ref.10e DAN SSSR, 1958, V'.1-22. No.lr,, 8o6,. 'rhe ava4lable data, x
obtained by X--ray methods, on b