SCIENTIFIC ABSTRACT LIVSHITS, B. G. - LIVSHITS, B. G.

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December 31, 1967
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SCIENTIFIC ABSTRACT
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Uri ar I tfx tat 1'E ll Ft F O I X oil r HUR! OUR 2 ;a 0 it SOUP E 129 F F Sri 1_4 Te'liii vip 1 0 il A a 13, 5711 to" go NER aw to P. 7 HO-ITHRE, Na goo ;L 0 @Pa n r, ;n r I El UR; Mal - holl -g Age! 0.10, -j" S- -2 -04 R. a as 0 2 ,a "Ol no rl),.!H 10. IRII 10 p '0" 0. ".1 i C', 05 .0. 8-0 03 i g" 6OUN or ;rr ZI ear, v 0 0 1. 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, Card 1/3 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 Card@2/6 3/148/60/OOCI/009/020/025 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 Card 3/6 3/148/60/000/009/020/025 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 Card 2/ ;5 20254 3/148/6o/ooo/oil/oil/015 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 Card 1/4 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 Card 1/3 S/180/61/000/005/014/oi8 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, Card-2/3 !5 16@0 - 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