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1.
L. V. Kuksa B. I. Koval'chuk A. A. Lebedev V. I. Él'manovich 《Strength of Materials》1976,8(4):393-398
1. | Plastic deformation in polycrystalline copper develops unevenly in the microregions in both the linear and the plane stress state (including plane stress under conditions of complex loading). A higher level of microinhomogeneity in deformation was observed in the plane stress state. |
2. | The immobilization and duplication of microcenters of increased and reduced deformation in simple loading is a general property of polycrystalline materials and is in independent of the nature of the material and the type of stress state. |
3. | The development of deformations in individual microsectors in conditions of complex loading (axial tension—uniform biaxial tension—transverse tension) differs substantially from that in simple loading. The difference lies in the varying degrees of localization of deformation of fixed microsectors. |
4. | In a plane stress state, especially under conditions of complex loading, deformation is due to the action of a larger number of slip systems than in a linear stress state; this must indicate more complex deformation conditions in the individual microvolumes. |
2.
S. B. Kasatkin 《Strength of Materials》1976,8(11):1346-1350
1. | Polycarbonate specimens enable direct observation of the stress-strain pattern during the loading process. |
2. | It has been shown that under plane strain and plane stress conditions the crack starts at the boundary of the elastic-plastic deformation zone at the moment when the normal stress component reaches the critical value. |
3. | Under plane strain conditions the value cr is determined by the yield point and the radius of the notch n. Under plane stress conditions the strip of plastic deformation functions, as a stress concentrator. Fracture occurs when the normal stress component at the boundary reaches the critical value. |
4. | During the intervals when the specimen is not loaded the plastically deformed zones act as concentrators of residual stress. When load is again applied there is interaction between the residual stresses and the externally induced stresses. |
3.
a) | The study describes the basic fracture micromechanisms of porous materials with dominantly ferritic matrix structures. |
b) | Quantitative fractography is used to describe the basic mechanisms of crack propagation in the porous body corresponding to the non-monotonous temperature dependence of fracture toughness values. |
c) | Behavior of fracture toughness values and relevant fracture micromechanisms indicate that the state of plane deformation in microvolumes in front of the crack tip cannot be reached at higher porosities and temperatures. This piece of information corresponds to the knowledge of independence of fracture toughness values of porous materials on the specimen thickness, as is presented in the literature [5]. |
4.
A. Ya. Krasovskii I. V. Orynyak A. V. Naumov V. N. Krasiko 《Strength of Materials》1989,21(5):585-590
1. | The flexibility of the contact-zone/block system is determined experimentally from impact tests. In the case when high loading rates are used and massive specimens are tested, plastic deformations develop in the contact zone; this leads to effective values on the low side. |
2. | The duration and total amplitude of the resultant KI-t and P-t curves for supportfree tests are determined primarily by the flexibility of the specimen, while their character (the number of peaks, and their amplitude) is determined by the ratios of the flexibilities of specimen and block. |
3. | A method of calculating KI for a support-free impact loading is theoretically substantiated and experimentally confirmed. |
4. | During the impact testing of specimens on supports, separation of the specimen from the supports occurs at the initial time, i.e., these tests are actually support-free at the initial time. The moment of repeated contact between the specimen and the supports of the impact-testing machine corresponds approximately to time required for the force to reach the local minium. |
5.
1. | As a result of introduction of the system, the possibility of loss of information on the vibration condition of an engine has been eliminated, especiallyin short time appearance of vibrations in failure situations when the vibrations increase very rapidly. |
2. | The measuring accuracy has been increased. |
3. | Recording of the parameters of vibrations in combination with other parameters characterizing the operation of the engine is provided. |
4. | The process of interpreting and treating the test results has been accelerated. |
6.
1. | The microstructure of the steel has a strong effect on the resistance to low-cycle fracture. The highest fracture resistance in cyclic loading is shown by the steel with the austenitic structure, that of the steel with the ferritic-pearlitic structure is slightly lower, whereas the lowest resistance was recorded for the steel of the transition grade (ferritic-martensitic). This is explained by special features of deformation of their microstructural components and different properties of the crystal lattice. |
2. | In low-cycle loading, the austenitic steel shows susceptibility to hardening, the steel of the ferritic-pearlitic grade is stable, and the steel with the sorbitic and ferritic-martensitic microstructure softens. |
3. | The low-cycle deformation resistance of the steels of different structural grades depends on the strength properties in static loading: the resistance is always higher In the material with a higher ultimate strength, i.e., in the steel with a martensitic microstructure. |
4. | The microstructure of the steel has the maximum effect in the near-threshold region of the fatigue failure diagram. |
7.
S. I. Yakovenko A. P. Guk V. I. Lakh V. N. Kryzhanovskii 《Strength of Materials》1988,20(12):1682-1684
1. | The temperature-time relationship of the allowable mechanical loads of a thermal transducer protection tube was established. |
2. | For a preliminary evaluation of the strength of a thermal transducer in relation to service time it is necessary to use the temperature relationship of the modulus of elasticity or of the stress-rupture strength of the materials used. |
3. | Failure of the protection tube of a thermal transducer in long high-temperature loading occurs as the result of development of pores primarily at grain boundaries. |
8.
1. | We proposed a method which can be used to examine the kinetics of failure and cracking resistance of the materials taking into account the type of thermal effect. |
2. | The results show that the variation of the temperature conditions during macrocrack propagation has a controlling effect on force and energy characteristics of failure and on the change of the failure micromechanisms. This effect differs for different types of materials. |
3. | Electron fractographic examination showed that the level and nature of damage in the material obtained in the previous stage of thermal loading greatly affects the relationships governing the propagation of the macrocrack after a temperature change. |
4. | It is shown that it is important to take into account the history of thermal loading (direction and temperature variation amplitude) in determining the cracking resistance of materials and structures. |
9.
Comparing the fracture toughness temperature curves evaluated at static and rapid loading on larger (SENB, 1CT) specimens with the fracture toughness curve determined on precracked Charpy specimens at impact loading, the following conclusions can be drawn:
Published in Fiziko-Khimiches-kaya Mekhanika Materialov, No. 3, pp. 54–60, May–June, 1992. 相似文献
| both rapid and impact loadings cause the shift of fracture toughness temperature curve to higher temperatures in accordance with the concept of critical tensile stress criterion; |
| the transition temperature region with brittle (cleavage) initiated fracture after some ductile crack growth is, at rapid loading, shifted to higher temperature as well; |
| at the impact loading of small PC specimens the whole transition region is reduced to one transition temperature only and therefore sharp increase from the lower shelf fracture toughness region to the upper one occurred. This ductile to cleavage initiation transition temperature is, in spite of the impact loading, lower than that of the larger 1CT specimens loaded at a much smaller loading rate; |
| for cleavage initiated fracture of low alloy steel only lower shelf fracture toughness values can be measured by employing the PC specimens and the impact loading. |
10.
1. | We derived an equation which can be used to determine the endurance in cyclic loading on the basis of the crack initiation criterion in elastoplastic deformation of the material and the triaxial stress state. | ||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||
2. | Rapid fatigue damage cumulation can take place in the material only if the size of the reversible elastoplastic zone is larger than the grain diameter. | ||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||
3. | The assumption on the homogeneity of SSS in the structural element makes it possible to describe most adequately the relationship between the strain and fatigue damage of the material. | ||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||
4. | We derived an analytical expression linking the threshold value of the stress intensity factor \GDKth with the mechanical properties and grain diameter of the material. | ||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||
5. |
A model of fatigue crack propagation which is based on the approximate analytical solution of the cyclic elastoplastic problem of the SSS in the vicinity of the crack tip was developed. The model takes into account the special features of deformation of the material in the conditions of the triaxial stress state and also uses the assumption on the homogeneity of SSS in the structural element. The main advantages of the model are as follows:
it can be used to determine the crack growth rate in cases in which the variation of the range of the stress intensity factor in the structural members takes place at the variable loading asymmetry; 相似文献
11.
A. Yu. Chirkov 《Strength of Materials》1988,20(9):1246-1258
12.
Abstract and Key Results
13.
B. A. Kolachev 《Materials Science》1992,28(5):395-398
14.
L. E. Matokhnyuk A. V. Voinalovich A. A. Khlyapov V. L. Belov A. B. Pavlova A. V. Kirillova 《Strength of Materials》1988,20(7):861-867
15.
Laszlo Tihanyi Robert E. Hoskisson Richard A. Johnson William P. Wan 《Management International Review》2009,49(4):409-431
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