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1.
1. | Rolling of steel at 1100° and higher leads to austenite grain growth after annealing. |
2. | A recrystallization threshold appears with plastic deformation at temperatures up to 1100°, the range of the recrystallization threshold broadening as the temperature of the preceding plastic deformation decreases. Plastic deformation =20% at 1150° always leads to a jump of austenite grain growth with repeated quenching, and for steel rolled at 1150 and 1200° the region of austenite grain growth broadens to =30–40%. |
3. | At all degrees of deformation at different temperatures the average diameter of austenite grains decreases with decreasing preliminary rolling temperatures and increasing degrees of repeated plastic deformation. This undoubtedly affects the consistency of the properties inherited by high-speed steel during subsequent high-temperature plastic deformation. |
2.
1. | The hot deformation of corrosion-resistant steels of the ferritic, austenitic, and austenitic—ferritic classes in the 900–1100°C interval at rates sec–1 results in dynamic recrystallization. |
2. | Various types of substructures are formed in the initial stages of plastic flow, depending on the deformation conditions and the type of crystal lattice of the steels, and, consequently, different mechanisms of dynamic recrystallization are realized. |
3. | Substructure formation in the initial grains and gradual transformation of low- to high-angle boundaries are the mechanisms responsible for the formation of recrystallized grains in the ferritic steels over the entire temperature region investigated, and in the austenitic-class steel at high temperatures. |
3.
L. M. Storozheva D. A. Burko E. M. Grinberg Yu. E. Rodionova R. Bode K. Esher 《Metal Science and Heat Treatment》2000,42(7):267-271
Conclusions
Translated from Metallovedenie i Ternicheskaya Obrabotka Metallov, No. 7, pp. 14–17, July, 2000. 相似文献
1. | Recrystallization of steels after hot rolling with a low reeling temperature begins and ends at a higher temperature and a longer hold than in steels obtained with reeling at a higher temperature. |
2. | After hot rolling with a high reeling temperature the recrystallization of steel not bearing excess elements in the solid solution (Nb/C ef ≅1) begins and ends much more rapidly than recrystallization in the other steels. |
3. | After continuous annealing, the ferrite grains in steel with Nb/C ef ≅1 have a maximumsize, which is connected with the leading recrystallization of this steel. |
4. | The growth of ferrite grains in steel subjected to high-temperature reeling is accompanied by a decrease in the yield point and an increase in the specific elongation and coefficient of normal plastic anisotropy. Steels with Nb/C ef ≅1 have maximum mechanical properties. |
4.
Conclusions
Translated from Metallovedenie i Termicheskaya Obrabotka Metallov, No. 5, pp. 20–23, May, 1999. 相似文献
1. | The structure of powder white iron at a content of carbide phase amounting to from 40 to 60% virtually does not change relative to the initial (annealed) state in the process of plastic deformation. |
2. | Hot plastic deformation without subsequent heat treatment affects the level of mechanical properties and the wear resistance of powder white iron comparatively weakly. |
3. | Heat treatment increases the level of mechanical properties and the relative wear resistance of powder white iron, the effect being the most significant at 2.5–3%C. |
5.
Conclusions
Translated from Metallovedenie i Termicheskaya Obrabotka Metallov, No. 11, pp. 21–25, November, 1999. 相似文献
1. | VChShG can be subjected to different kinds of plastic deformation without failure. |
2. | In the process of plastic deformation of cast VChShG, graphite inclusions irreversibly lose their globular shape, extending along the direction of metal flow in the deformation source. Subsequent heat treatment affects only the microstructure and the morphology of the phases that compose the metallic matrix and does not affect the shape of graphite inclusions. This determines the level and the isotropic nature of the mechanical properties of semifinished products of VChShG fabricated by plastic deformation of cast preforms and imposes certain constraints on the production process and the quality parameters of ready articles. |
3. | VChShG are susceptible to decarburization of the surface layer in heat treatment or heating for deformation in a furnace with an oxidizing atmosphere, which should be taken into account in designing the method of their deformation. |
6.
1. | Recrystallization of deformed ferrite in steel R6M5 commences at about 780°C and it continues to the maximum recrystallization temperatures for existence of -solid solution. The temperature ranges for recrystallization and superplasticity coincide. |
2. | Dynamic recrystallization of ferrite in steel R6M5 with rolling for one pass is incomplete with all degrees of deformation. |
3. | Static recrystallization occurs entirely with 50%. The recrystallized ferrite grain size is finer than the original by a factor of four to five. |
4. | Polygonization of deformed ferrite may markedly stabilize the structure and there-by make recrystallization difficult. |
7.
M. E. Smagorinskii 《Metal Science and Heat Treatment》1989,31(7):539-544
1. | Thermal cycling treatment leads to more dispersed precipitation of hardening phases in comparison with artificial aging of the same length as the thermal cycling treatment. |
2. | The level of properties after thermal cycling treatment depends little upon the intensity of the thermal cycles. |
3. | Thermal cycling treatment of wrought alloys of the Al-Mg-Si system increases their toughness and plastic properties (by 1.5–2.0 times) while the strength characteristics are somewhat lower than after T1 treatment. |
4. | The cycles of mechanical-thermal cycling treatment including hardening, cold plastic deformation in the freshly hardened condition, and thermal cycling treatment make it possible to obtain high strength and electrical conductivity, the level of which depends upon the degree of deformation, the parameters of the thermal cycles, and the hold time at the maximum thermal cycle temperature. |
5. | Low-temperature thermal cycling treatment including hardening and repeated deformation with thermal cycles in the intervals between passes is promising for treatment of aluminum alloys. |
8.
O. M. Khovova O. M. Zhigalina I. O. Dumanskii V. G. Leshkovtsev 《Metal Science and Heat Treatment》2000,42(6):214-220
Conclusions
Translated from Metallovedenie i Termicheskaya Obrabotka Metallov, No. 6, pp. 13–19, June, 2000. 相似文献
1. | The dissolution of the excess Laves phase in alloy 36NKhTYuM8 under the conditions of rapid quenching is maximum in the stage of heating to 1200°C, and the efficiency of the treatment increases in proportion to the heating rate. We have suggested an explanation of the determining role of the heating rate in the dissolution of the excess phase, which is based on the concept of high thermal stresses that appear on the interphase boundaries because of the difference in the coefficients of thermal expansion of the matrix and the phase. |
2. | High plastic deformation of alloy 36NKhTYuM8 (ε=70%) is accompanied by deformation and cracking of the particles of the excess Laves phase, but the nonequilibrium nature of the structure of these particles does not influence noticeably their solubility under the conditions of rapid heating. |
3. | The process of primary recrystallization that occurs in deformed alloy in the stage of rapid heating does not stimulate the dissolution of the excess phase, which means that the efficiency of rapid heating in quenching of alloys can be used independently of their initial state. |
9.
1. | The presence of large grains on the surfaces of parts made from plates produced at the Zaporozhstal' Factory and annealed at 800\dg is due to the critical degree of rolling reduction. | ||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||
2. |
The critical degree of rolling reduction leads to grain growth as the result of secondary recrystallization in the process of annealing at 800°.
It is recommended that plates be subjected to recrystallization annealing at 600°. 相似文献
10.
S. B. Maslenkov I. V. Kabanov E. A. Maslenkova O. V. Abramov I. N. Mel'kumov 《Metal Science and Heat Treatment》1991,33(10):748-752
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Conclusions
13.
T. S. Dolotova V. I. Kucheryavyi N. V. Ul'yanova 《Metal Science and Heat Treatment》1976,18(9):786-789
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16.
G. N. Kadykova T. K. Lyakhovich I. I. Khvostikova 《Metal Science and Heat Treatment》1992,34(1):77-80
17.
V. V. Medvedev B. V. Mochalov Yu. B. Sazonov L. G. Chernukha I. P. Ezhov 《Metal Science and Heat Treatment》1999,41(4):151-153
Conclusions
18.
Conclusions
19.
V. N. Semenov 《Metal Science and Heat Treatment》1999,41(10):441-445
20.
S. B. Maslenkov I. V. Kabanov I. N. Mel'kumov E. A. Maslenkova S. P. Barabanov 《Metal Science and Heat Treatment》1992,34(1):20-25
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