Journal articles: 'Brittle-ductile transition'

1

Ross, John V., and Peter D. Lewis. "Brittle-ductile transition: semi-brittle behavior." Tectonophysics 167, no. 1 (October 1989): 75–79. http://dx.doi.org/10.1016/0040-1951(89)90295-3.

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2

Christensen, Richard M. "The ductile/brittle transition provides the critical test for materials failure theory." Proceedings of the Royal Society A: Mathematical, Physical and Engineering Sciences 474, no. 2210 (February 2018): 20170817. http://dx.doi.org/10.1098/rspa.2017.0817.

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It is reasoned that any materials failure theory that claims generality must give full account of ductile versus brittle failure behaviour. Any such proposed theory especially must admit the capability to generate the ductile/brittle transition. A derivation of the failure surface orientations from a particular isotropic materials failure theory reveals that uniaxial tension has its ductile/brittle transition at T / C = 1/2, where T and C are the uniaxial strengths. Between this information and the corresponding ductile/brittle transition in uniaxial compression it becomes possible to derive the functional form for the fully three-dimensional ductile/brittle transition. These same general steps of verification must be fulfilled for any other candidate general failure theory.

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3

Huo, Feng Wei, Zhu Ji Jin, Fu Ling Zhao, Ren Ke Kang, and Dong Ming Guo. "Experimental Investigation of Brittle to Ductile Transition of Single Crystal Silicon by Single Grain Grinding." Key Engineering Materials 329 (January 2007): 433–38. http://dx.doi.org/10.4028/www.scientific.net/kem.329.433.

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Grinding of single crystal silicon may be achieved by two modes of material removal: ductile mode and brittle mode. Knowing of the brittle to ductile transition point at which the grinding process changes from the brittle mode to ductile mode is critically important for the realization of ductile mode grinding. This paper uses a new single grain diamond grinding method developed recently by the authors to investigate the brittle to ductile transition during grinding of single crystal silicon in all around. The results indicate that there exist four stages of brittle to ductile transition as the depth of cut is reduced: firstly, the surface cracks outside the grinding groove disappeared, secondlycracks on the bottom of the groove disappeared, then the lateral cracks ceased in the subsurface region, and finally the median crack is suppressed beneath the grooves. It is not until the depth of cut reaches the last transition point that a crack-free groove can be produced, therefore, the last transition stage is decisive. The critical depth of cut delineating the brittle to ductile transition point derived based on this criterion is 40 nanometers, which is much lower than that based on surface cracks.

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4

TANAKA, Yoshio, Kazuo MURATA, Katsumi MIZUTANI, and Okito OGASAWARA. "Ductile/Brittle Transition of Brittle Materials in Indentation." Journal of the Society of Materials Science, Japan 51, no. 5 (2002): 555–60. http://dx.doi.org/10.2472/jsms.51.555.

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5

Zhang, Guang, Jing Xi Chen, and Bin Hu. "The Brittle-Ductile Transition Character of Rocks and Its Effect on Rockbursts." Key Engineering Materials 261-263 (April 2004): 171–76. http://dx.doi.org/10.4028/www.scientific.net/kem.261-263.171.

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The brittle-ductile character is one of the important mechanical indexes of rocks and also one of the important affecting factors of rockburst. Both conventional and true triaxial tests have shown that the brittle-ductile character of rocks varies with the variation in rocks stress state and stress path, but these two kinds of tests have revealed totally different laws of brittle-ductile transition. This present paper analyses the results from two tests firstly and then summarizes the effect of rock’s brittle-ductile transition character on rockburst and finally points out the deficiency in present studies of rockburst.

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6

Hirsch, Sir Peter B. "Fundamentals of the Brittle-Ductile Transition." Materials Transactions, JIM 30, no. 11 (1989): 841–55. http://dx.doi.org/10.2320/matertrans1989.30.841.

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7

Hirsch, Peter B. "Fundamentals of the brittle-ductile transition." Bulletin of the Japan Institute of Metals 29, no. 1 (1990): 5–17. http://dx.doi.org/10.2320/materia1962.29.5.

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8

Maeda, Koji, Shinobu Fujita, Hiroyuki Nishioka, and Takenori Narita. "Brittle-ductile transition in covalent crystals." Bulletin of the Japan Institute of Metals 29, no. 12 (1990): 999–1007. http://dx.doi.org/10.2320/materia1962.29.999.

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9

Hirsch, P. B., and S. G. Roberts. "The brittle-ductile transition in silicon." Philosophical Magazine A 64, no. 1 (July 1991): 55–80. http://dx.doi.org/10.1080/01418619108206126.

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10

Lyu, Su-Ping, Xiao-Guang Zhu, and Zong-Neng Qi. "Brittle-ductile transition of polymer blends." Journal of Polymer Research 2, no. 4 (October 1995): 217–24. http://dx.doi.org/10.1007/bf01492773.

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11

Huang, Z., and M. Yao. "Research into brittle/ductile transition temperature." Scripta Metallurgica 23, no. 12 (December 1989): 2137–42. http://dx.doi.org/10.1016/0036-9748(89)90246-9.

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12

Tóth, L. "Notch effect and brittle-ductile transition." Materials Science 34, no. 5 (September 1998): 619–29. http://dx.doi.org/10.1007/bf02355780.

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13

Cooper, Frances J., John P. Platt, and Whitney M. Behr. "Rheological transitions in the middle crust: insights from Cordilleran metamorphic core complexes." Solid Earth 8, no. 1 (February 21, 2017): 199–215. http://dx.doi.org/10.5194/se-8-199-2017.

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Abstract. High-strain mylonitic rocks in Cordilleran metamorphic core complexes reflect ductile deformation in the middle crust, but in many examples it is unclear how these mylonites relate to the brittle detachments that overlie them. Field observations, microstructural analyses, and thermobarometric data from the footwalls of three metamorphic core complexes in the Basin and Range Province, USA (the Whipple Mountains, California; the northern Snake Range, Nevada; and Ruby Mountains–East Humboldt Range, Nevada), suggest the presence of two distinct rheological transitions in the middle crust: (1) the brittle–ductile transition (BDT), which depends on thermal gradient and tectonic regime, and marks the switch from discrete brittle faulting and cataclasis to continuous, but still localized, ductile shear, and (2) the localized–distributed transition, or LDT, a deeper, dominantly temperature-dependent transition, which marks the switch from localized ductile shear to distributed ductile flow. In this model, brittle normal faults in the upper crust persist as ductile shear zones below the BDT in the middle crust, and sole into the subhorizontal LDT at greater depths.In metamorphic core complexes, the presence of these two distinct rheological transitions results in the development of two zones of ductile deformation: a relatively narrow zone of high-stress mylonite that is spatially and genetically related to the brittle detachment, underlain by a broader zone of high-strain, relatively low-stress rock that formed in the middle crust below the LDT, and in some cases before the detachment was initiated. The two zones show distinct microstructural assemblages, reflecting different conditions of temperature and stress during deformation, and contain superposed sequences of microstructures reflecting progressive exhumation, cooling, and strain localization. The LDT is not always exhumed, or it may be obscured by later deformation, but in the Whipple Mountains, it can be directly observed where high-strain mylonites captured from the middle crust depart from the brittle detachment along a mylonitic front.

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14

IKESHOJI, TOSHITAKA, and TADASHI SHIOYA. "BRITTLE-DUCTILE TRANSITION AND SCALE DEPENDENCE: FRACTAL DIMENSION OF FRACTURE SURFACE OF MATERIALS." Fractals 07, no. 02 (June 1999): 159–68. http://dx.doi.org/10.1142/s0218348x99000189.

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The fractal dimension of fracture surfaces obtained within brittle-ductile transition regime is evaluated at various observation scales. Fracture surfaces are generated by the tensile fracture test. The brittle-ductile transition is accomplished by using the round-notched bar specimens with various notch radii, which cause the variation in stress triaxiality. The specimens are manufactured from mild steel, steel and cast-iron bar. The fracture model is identified according to the observation through scanning electron micrographs. The fractal dimension for ductile fracture surfaces is almost constant despite variations in observing scale and changes in stress triaxiality. Meanwhile, the fractal dimension on brittle fracture surfaces shows the different values for macroscopic and microscopic observing scales. This transition-like scale dependence of fractal dimension for brittle fracture surfaces is considered to reflect such a characteristic of the fracture i.e. its specific length in microscopic fracture mechanism. The existence of transition in fractal dimension with observing scale is considered to be an index, used to distinguish the ductile fracture surface from the brittle fracture one.

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15

Oncken, Onno. "Fold mimicry - tectonic overprinting of sedimentary structures in the brittle-ductile transition." Neues Jahrbuch für Geologie und Paläontologie - Monatshefte 1986, no. 12 (December 31, 1986): 723–35. http://dx.doi.org/10.1127/njgpm/1986/1986/723.

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16

Semenov, Ya S. "Theory of ductile-brittle transitions in steels and iron alloys: Substantiation of the ductile-brittle transition mechanism." Doklady Physical Chemistry 416, no. 2 (December 2007): 289–91. http://dx.doi.org/10.1134/s0012501607100065.

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17

Hagiwara, Naoto, Tomoki Masuda, and Noritake Oguchi. "Effects of Prestrain on Fracture Toughness and Fatigue-Crack Growth of Line Pipe Steels." Journal of Pressure Vessel Technology 123, no. 3 (April 20, 2001): 355–61. http://dx.doi.org/10.1115/1.1379531.

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Crack-tip-opening displacement (CTOD) and fatigue-crack growth tests were conducted for several line pipe steels with uniaxial tensile or compressive prestrain, εpr. Critical CTOD decreased with increasing |εpr|. The reduction of critical CTOD due to prestrain was dependent on the ductile-brittle transition temperature of the steels without prestrain. A few percent of εpr induced the ductile-brittle transition for the steels with a higher transition temperature. The compressive εpr had larger effects on both reduction of critical CTOD and strain induced ductile-brittle transition than the tensile εpr. Only the high compressive εpr accelerated both fatigue crack initiation and growth, and no obvious effect of the tensile εpr on the fatigue properties was observed.

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18

Seok, Chang Sung, Hyung Ick Kim, Dae Jin Kim, Bong Kook Bae, and Sang Pil Kim. "Evaluation of Ductile-Brittle Transition of Fracture Toughness by Material Degradation." Key Engineering Materials 297-300 (November 2005): 2465–70. http://dx.doi.org/10.4028/www.scientific.net/kem.297-300.2465.

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When huge energy transfer systems like nuclear power plants and steam power plants are operated for long times at high temperatures, mechanical properties change and ductile-brittle transition temperature increases by degradation. So we must estimate the degradation in order to assess safety, life expectancy, and other operation parameters. The sub-sized specimen test method using the surveillance specimen, and BI (Ball Indentation) method were developed for evaluating the integrity of metallic components. In this study, we will present the evaluation of the ductile-brittle transition temperature using the BI test and the sub-sized specimen test. The four classes of the thermally aged 1Cr-1Mo-0.25V specimens were prepared using an artificially accelerated aging method. The tensile test, the fracture toughness test, and the BI test were performed. The results of the fracture toughness tests using the sub-sized specimens were compared with those of the BI test. The evaluation technique of the ductile-brittle transition temperature using the BI test was also discussed. Our results show that the ductile-brittle transition temperatures rose as the aging time increased. We suggested that the fracture toughness results of the sub-sized specimen test and the IEF results of the BI test could be used in the estimation of the ductile-brittle transition temperature as material degrades.

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19

Dow, Thomas A., and Ronald O. SCATTERGOOD. "Ductile/brittle transition and development of ductile mode grinding technology." Journal of the Japan Society for Precision Engineering 56, no. 5 (1990): 794–99. http://dx.doi.org/10.2493/jjspe.56.794.

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20

Gumbsch, Peter. "Brittle fracture and the brittle-to-ductile transition of tungsten." Journal of Nuclear Materials 323, no. 2-3 (December 2003): 304–12. http://dx.doi.org/10.1016/j.jnucmat.2003.08.009.

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21

Zou, H. F., and Z. F. Zhang. "Ductile-to-brittle transition induced by increasing strain rate in Sn–3Cu/Cu joints." Journal of Materials Research 23, no. 6 (June 2008): 1614–17. http://dx.doi.org/10.1557/jmr.2008.0214.

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The current study revealed the effects of strain rate on tensile strength and ductile-to-brittle transition of Sn–3Cu/Cu joints in the strain rate range of 4.2 × 10−5 to 2.4 × 10−1 s−1. Experimental results indicate that these joints broke in a ductile manner at low strain rates with a rapid increase in the tensile strength but displayed a brittle manner at higher strain rates with a slow increase in the tensile strength, indicating a typical ductile-to-brittle transition feature. A method was proposed to estimate the interfacial strength between the solder and the intermetallic compounds.

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22

Meyer, Gabriel G., Nicolas Brantut, Thomas M. Mitchell, and Philip G. Meredith. "Fault reactivation and strain partitioning across the brittle-ductile transition." Geology 47, no. 12 (October 16, 2019): 1127–30. http://dx.doi.org/10.1130/g46516.1.

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Abstract The so-called “brittle-ductile transition” is thought to be the strongest part of the lithosphere, and defines the lower limit of the seismogenic zone. It is characterized not only by a transition from localized to distributed (ductile) deformation, but also by a gradual change in microscale deformation mechanism, from microcracking to crystal plasticity. These two transitions can occur separately under different conditions. The threshold conditions bounding the transitions are expected to control how deformation is partitioned between localized fault slip and bulk ductile deformation. Here, we report results from triaxial deformation experiments on pre-faulted cores of Carrara marble over a range of confining pressures, and determine the relative partitioning of the total deformation between bulk strain and on-fault slip. We find that the transition initiates when fault strength (σf) exceeds the yield stress (σy) of the bulk rock, and terminates when it exceeds its ductile flow stress (σflow). In this domain, yield in the bulk rock occurs first, and fault slip is reactivated as a result of bulk strain hardening. The contribution of fault slip to the total deformation is proportional to the ratio (σf − σy)/(σflow − σy). We propose an updated crustal strength profile extending the localized-ductile transition toward shallower regions where the strength of the crust would be limited by fault friction, but significant proportions of tectonic deformation could be accommodated simultaneously by distributed ductile flow.

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23

Zhao, Wei, Haibo Hong, and Hongzhi Wang. "Mechanism of Unstable Material Removal Modes in Micro Cutting of Silicon Carbide." Micromachines 10, no. 10 (October 13, 2019): 696. http://dx.doi.org/10.3390/mi10100696.

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This study conducts large-scale molecular dynamics (MD) simulations of micro cutting of single crystal 6H silicon carbide (SiC) with up to 19 million atoms to investigate the mechanism of unstable material removal modes within the transitional range of undeformed chip thickness in which either brittle or ductile mode of cutting might occur. Under this transitional range, cracks are always formed in the cutting zone, but the stress states cannot guarantee their propagation. The cutting mode is brittle when the cracks can propagate and otherwise ductile mode cutting happens. Plunge cutting experiment is conducted to produce a taper groove on a 6H SiC wafer. There is a transitional zone between the brittle-cut and ductile-cut regions, which has a mostly smooth surface with a few brittle craters on it. This study contributes to the understanding of the detailed process of brittle-ductile cutting mode transition (BDCMT) as it shows that a transitional range can occur even for single crystals without internal defects and provides guidance for the determination of tcritical from taper grooves made by various techniques, e.g., to adopt larger tcritical around the end of the transitional range to increase machining efficiency for grinding or turning as long as the cracks do not extend below the machined surface.

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24

George, A. "Introducing Brittle-Ductile Transition and Interfacial Debonding." Solid State Phenomena 59-60 (January 1998): 251–72. http://dx.doi.org/10.4028/www.scientific.net/ssp.59-60.251.

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25

Maeda, Koji. "Brittle-Ductile Transition Controlled by Dislocation Mobility." Materia Japan 36, no. 3 (1997): 206–10. http://dx.doi.org/10.2320/materia.36.206.

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26

Li, Rong, and K. Sieradzki. "Ductile-brittle transition in random porous Au." Physical Review Letters 68, no. 8 (February 24, 1992): 1168–71. http://dx.doi.org/10.1103/physrevlett.68.1168.

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27

Morozov, N. F., Yu V. Petrov, and V. I. Smirnov. "Transition between brittle and ductile erosional fracture." Doklady Physics 47, no. 7 (July 2002): 525–27. http://dx.doi.org/10.1134/1.1499192.

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28

Menezes-Sobrinho, Ismael L., José-Guilherme Moreira, and Américo T. Bernardes. "Brittle-Ductile Transition in Fiber-Reinforced Composites." International Journal of Modern Physics C 09, no. 06 (September 1998): 851–56. http://dx.doi.org/10.1142/s0129183198000789.

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Fiber-reinforced composites are a class of material with increasing industrial applications. Computer simulations have been used in order to understand the microscopic mechanism which can explain their mechanical behavior and several models have been introduced in the last decade. In this paper we introduce a criterion to define the brittle-ductile transition region in unidirectional fiber-reinforced composites. In order to simulate a fiber bundle, a recently introduced stochastic model is used. The results obtained with our criterion are compared with those obtained by using a self-organized criticality (SOC) approach.

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29

Sun, Y. H. "Inverse ductile–brittle transition in metallic glasses?" Materials Science and Technology 31, no. 6 (October 10, 2014): 635–50. http://dx.doi.org/10.1179/1743284714y.0000000684.

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30

Needleman, A. "Numerical Modeling of the Ductile-Brittle Transition." Le Journal de Physique IV 06, no. C6 (October 1996): C6–325—C6–334. http://dx.doi.org/10.1051/jp4:1996632.

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31

Campbell, Geoffrey H., Brian J. Dalgleish, and Anthony G. Evans. "Brittle-to-Ductile Transition in Silicon Carbide." Journal of the American Ceramic Society 72, no. 8 (August 1989): 1402–8. http://dx.doi.org/10.1111/j.1151-2916.1989.tb07661.x.

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32

Ebrahimi, F., and T. G. Hoyle. "Brittle-to-ductile transition in polycrystalline NiAl." Acta Materialia 45, no. 10 (October 1997): 4193–204. http://dx.doi.org/10.1016/s1359-6454(97)00090-6.

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33

Yang, Fan, and Wei Yang. "Brittle versus ductile transition of nanocrystalline metals." International Journal of Solids and Structures 45, no. 13 (June 2008): 3897–907. http://dx.doi.org/10.1016/j.ijsolstr.2007.12.018.

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34

Brede, M. "The brittle-to-ductile transition in silicon." Acta Metallurgica et Materialia 41, no. 1 (January 1993): 211–28. http://dx.doi.org/10.1016/0956-7151(93)90353-t.

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35

Serbena, F. C., and S. G. Roberts. "The brittle-to-ductile transition in germanium." Acta Metallurgica et Materialia 42, no. 7 (July 1994): 2505–10. http://dx.doi.org/10.1016/0956-7151(94)90331-x.

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36

Carpinteri, A., C. Marega, and A. Savadori. "Ductile-brittle transition by varying structural size." Engineering Fracture Mechanics 21, no. 2 (January 1985): 263–71. http://dx.doi.org/10.1016/0013-7944(85)90015-3.

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37

Samuels, J., S. G. Roberts, and P. B. Hirsch. "The brittle-to-ductile transition in silicon." Materials Science and Engineering: A 105-106 (November 1988): 39–46. http://dx.doi.org/10.1016/0025-5416(88)90478-8.

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38

Argon, A. S. "Brittle to ductile transition in cleavage fracture." Acta Metallurgica 35, no. 1 (January 1987): 185–96. http://dx.doi.org/10.1016/0001-6160(87)90228-8.

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39

Cornwell, Charles F., and Charles R. Welch. "Brittle ductile transition in carbon nanotube bundles." Molecular Simulation 38, no. 13 (November 2012): 1032–37. http://dx.doi.org/10.1080/08927022.2012.685940.

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40

Harada, Y., and M. Ohmori. "Ductile–brittle transition behavior of rolled chromium." Journal of Materials Processing Technology 153-154 (November 2004): 93–99. http://dx.doi.org/10.1016/j.jmatprotec.2004.04.011.

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41

Li, H., and F. Ebrahimi. "Ductile-to-Brittle Transition in Nanocrystalline Metals." Advanced Materials 17, no. 16 (August 18, 2005): 1969–72. http://dx.doi.org/10.1002/adma.200500436.

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42

Lavier, Luc L., Richard A. Bennett, and Ravindra Duddu. "Creep events at the brittle ductile transition." Geochemistry, Geophysics, Geosystems 14, no. 9 (September 2013): 3334–51. http://dx.doi.org/10.1002/ggge.20178.

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43

Mandelkern, L., F. L. Smith, M. Failla, M. A. Kennedy, and A. J. Peacock. "The brittle-ductile transition in linear polyethylene." Journal of Polymer Science Part B: Polymer Physics 31, no. 4 (March 30, 1993): 491–93. http://dx.doi.org/10.1002/polb.1993.090310416.

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44

Bayu-Aji, Leonardus B., and P. Pirouz. "Brittle-to-ductile transition temperature in InP." physica status solidi (a) 207, no. 5 (December 14, 2009): 1190–95. http://dx.doi.org/10.1002/pssa.200925347.

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45

Zhao, Ya-Pu. "Irwin number and ductile-brittle fracture transition." International Journal of Fracture 75, no. 1 (1996): R17—R21. http://dx.doi.org/10.1007/bf00018531.

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46

Hwang, Byoung Chul, Tae Ho Lee, Seong Jun Park, Chang Seok Oh, and Sung Joon Kim. "Ductile-to-Brittle Transition Behavior of High-Nitrogen 18Cr-10Mn-0.35N Austenitic Steels Containing Ni and Cu." Materials Science Forum 654-656 (June 2010): 158–61. http://dx.doi.org/10.4028/www.scientific.net/msf.654-656.158.

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Ductile-to-brittle transition behavior of high-nitrogen 18Cr-10Mn-0.35N austenitic steels containing Ni and Cu was investigated by means of Charpy impact test and fractographic analysis. The commonly observed fracture mode of the specimens tested at -196 oC was transgranular cleavage-like brittle with flat facets occurring along {111} crystallographic planes, thereby leading to the occurrence of ductile-to-brittle transition. For all the steels investigated in the present study, the ductile-to-brittle transition temperature (DBTT) measured from Charpy impact tests was much higher by 90 to 135 oC than that predicted by empirical equation strongly depending on N content. The combined addition of Ni and Cu enabled the 18Cr-10Mn-0.35N steels to have the lowest DBTT, which could be explained by relatively high austenite stability and favorable effect of Cu as well as the absence of delta-ferrite.

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47

Shamim, Shahrukh, Gaurav Sharma, and Chandrabalan Sasikumar. "The Effect of Intermetallic Phases on Ductile to Brittle Transition of Aluminium-Iron Alloy." Applied Mechanics and Materials 592-594 (July 2014): 770–75. http://dx.doi.org/10.4028/www.scientific.net/amm.592-594.770.

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The effect of intermetallic phases and grain size on ductile to brittle transition temperature of Aluminium-Iron alloy (Al–11% Fe) was investigated in this research work. An Izod impact testing method was adopted to study the DBTT in the temperature interval of 77 K to 373 K. The ductile-brittle transition points: fracture transition plastic (FTP), fracture-appearance transition temperature (FATT), impact energy transition temperature (IETT), fractional surface area of cleavage (brittle) and fibrous (ductile) fractures and grain size of the samples were also determined. The fracture toughness of Al-Fe alloy found decreasing with temperature in contrast to conventional materials. The fractographic investigation revealed that the microstructural changes play a major role in determining the fracture toughness of these alloys. Annealing of these samples slightly improved the fracture toughness as the spherical morphology of intermetallic particles resists the crack propagation.

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48

Chen, Ming, Qing Long An, Wei Min Lin, and Hitoshi Ohmori. "Fundamentals of BK7 Glass Removal in Micro/Nano-Machining." Advanced Materials Research 76-78 (June 2009): 485–90. http://dx.doi.org/10.4028/www.scientific.net/amr.76-78.485.

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The confine of ductile-mode cutting and brittle-mode cutting seems to be a crucial step for designing a brittle material removal process. However, the existing transition from ductile-mode to brittle-mode for BK7 material makes the confine of different mode very difficult. Through a series of micro/nano-machining tests, measurements of cutting forces and morphological appearance of cutting groove as well as the cross section at the certain depth of cut, the confirmation of ductile-mode cutting, transition-mode cutting and brittle-mode cutting has been clearly described in the paper. This lays a foundation for the fundamental understanding of cutting physics concerning of material characteristics and cutting tools, and thereafter for the development of optimal process technology.

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49

Blackley, W. S., and R. O. Scattergood. "Chip Topography for Ductile-Regime Machining of Germanium." Journal of Engineering for Industry 116, no. 2 (May 1, 1994): 263–66. http://dx.doi.org/10.1115/1.2901940.

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Ductile-regime response during the diamond turning of brittle germanium crystals is evident from the damage-free surfaces obtained. The nature of the ductile-regime processes cannot be determined by examination of the final machined surface itself. Machining chips were characterized using scanning electron microscopy. The chip topography provides insight into the ductile-to-brittle transition that occurs along the tool nose. A detailed examinaiton of the chips provides an independent estimate of the critical cutting depth for the transition.

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50

Yao, Peng, Wei Wang, Chuan Zhen Huang, Jun Wang, Hong Tao Zhu, and Tunemoto Kuriyagawa. "Indentation Crack Initiation and Ductile to Brittle Transition Behavior of Fused Silica." Advanced Materials Research 797 (September 2013): 667–72. http://dx.doi.org/10.4028/www.scientific.net/amr.797.667.

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To provide a fundamental knowledge for the high efficiency grinding and ultra-precision grinding of fused silica, ductile mode and brittle mode material removal mechanisms were investigated by conducting micro/nanoindentation experiments in the range of 4.9 mN - 1960 mN. Before observing cracks and determining the ductile to brittle transition penetration depth, the samples were etched with hydrofluoric acid to expose cracks. The typical damage morphology of fused silica was discussed by observing the surface and cross-section of indentations, and the depth of SSD was found to be determined by the cone cracks or borderline cracks in the different load range. The ductile to brittle transition penetration depth of fused silica under Vickers indentation was 180 nm.

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Journal articles on the topic 'Brittle-ductile transition'

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