Artículos de revistas: "Precipitation hardeninig"

1

Ardell, A. J. "Precipitation hardening". Metallurgical Transactions A 16, n.º 12 (diciembre de 1985): 2131–65. http://dx.doi.org/10.1007/bf02670416.

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2

Starink, Marco J. "Modelling of Precipitation Hardening in Alloys: Effective Analytical Submodels for Impingement and Coarsening". Materials Science Forum 539-543 (marzo de 2007): 2365–70. http://dx.doi.org/10.4028/www.scientific.net/msf.539-543.2365.

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To predict strength evolution of precipitation hardening alloys, a wide range of modelling approaches have been proposed. The most accurate published models are physics-based approaches which use both nanoscale processes with their related constants and parameters, as well as parameters calibrated to one or more macroscale measurements of yield strength of one or more samples. Recent developments in submodels including analytical expressions for volume fraction and size evolution including impingement and coarsening are reviewed. It is also shown that Kampmann-Wagner and JMAK models are generally not consistent with data on the progress of precipitations in the main precipitation hardening Al alloys systems, and improved model formulations are described.

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3

NIU, Jing. "Precipitation-hardening and toughness of precipitation-hardening stainless steel FV520(B)". Chinese Journal of Mechanical Engineering 43, n.º 12 (2007): 78. http://dx.doi.org/10.3901/jme.2007.12.078.

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4

Gladman, T. "Precipitation hardening in metals". Materials Science and Technology 15, n.º 1 (enero de 1999): 30–36. http://dx.doi.org/10.1179/026708399773002782.

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5

Furui, Mitsuaki, Susumu Ikeno y Seiji Saikawa. "Intragranular and Grain Boundary Precipitations with Aging Treatment in Mg-Al System Alloys Poured into Gravity Mold". Materials Science Forum 706-709 (enero de 2012): 1140–45. http://dx.doi.org/10.4028/www.scientific.net/msf.706-709.1140.

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It is well-known that age hardening occurs in Mg-Al system alloys, when the alloy containing aluminum exceeds 6mass%. This precipitation reaction depends on aluminum content and aging temperature. The aging behavior in AZ91 magnesium alloy was investigated and it is the subject of this paper. However, for the Mg-Al system alloys, the influence of aluminum content on aging hardening characteristics has not been researched in detail so far. In this study, continuous and discontinuous precipitations during aging in Mg-Al system alloys cast into sand and iron molds were investigated by means of hardness measurement and microstructure observation with optical microscopy and transmission electron microscopy. Variation of hardness with aging was found to be caused mainly by the discontinuous precipitation along the grain boundaries from the composite rule in hardness. In iron mold castings, It was found that the variation of hardness with aging was found to be caused mainly by the continuous precipitation inside the crystal grain.

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6

Herrnring, Jan, Nikolai Kashaev y Benjamin Klusemann. "Precipitation Kinetics of AA6082: An Experimental and Numerical Investigation". Materials Science Forum 941 (diciembre de 2018): 1411–17. http://dx.doi.org/10.4028/www.scientific.net/msf.941.1411.

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The development of simulation tools for bridging different scales are essential for understanding complex joining processes. For precipitation hardening, the Kampmann-Wagner numerical model (KWN) is an important method to account for non-isothermal second phase precipitation. This model allows to describe nucleation, growth and coarsening of precipitation hardened aluminum alloys based on a size distribution for every phase which produces precipitations. In particular, this work investigates the performance of a KWN model by [1-3] for Al-Mg-Si-alloys. The model is compared against experimental data from isothermal heat treatments taken partially from [2]. Additionally, the model is used for investigation of the precipitation kinetics for a laser beam welding process, illustrating the time-dependent development of the different parameters related to the precipitation kinetics and the resulting yield strength.

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7

Hornbogen, Erhard. "Hundred years of precipitation hardening". Journal of Light Metals 1, n.º 2 (mayo de 2001): 127–32. http://dx.doi.org/10.1016/s1471-5317(01)00006-2.

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8

Militzer, Matthias, Warren J. Poole y Weiping Sun. "Precipitation hardening of HSLA steels". Steel Research 69, n.º 7 (julio de 1998): 279–85. http://dx.doi.org/10.1002/srin.199805550.

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9

Shaikh, M. A., M. Ahmad, K. A. Shoaib, J. I. Akhter y M. Iqbal. "Precipitation hardening in Inconel*625". Materials Science and Technology 16, n.º 2 (febrero de 2000): 129–32. http://dx.doi.org/10.1179/026708300101507613.

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10

Zhao, Changhao, Shuang Gao, Tiannan Yang, Michael Scherer, Jan Schultheiß, Dennis Meier, Xiaoli Tan et al. "Precipitation Hardening in Ferroelectric Ceramics". Advanced Materials 33, n.º 36 (24 de julio de 2021): 2102421. http://dx.doi.org/10.1002/adma.202102421.

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11

Nie, J. F. y B. C. Muddle. "High temperature precipitation hardening in a rapidly quenched AlTiNi alloy I. Precipitation hardening response". Materials Science and Engineering: A 221, n.º 1-2 (diciembre de 1996): 11–21. http://dx.doi.org/10.1016/s0921-5093(96)10467-6.

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12

Senuma, Takehide y Yoshito Takemoto. "Influence of Alloying Elements on Precipitation Behavior of VCN in Middle Carbon Steels". Solid State Phenomena 172-174 (junio de 2011): 408–13. http://dx.doi.org/10.4028/www.scientific.net/ssp.172-174.408.

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For lightening the hot forged automotive components such as connecting rods, crank shafts etc. the increase in their yield strength is an important technical issue. Recent developments indicate that it is a promising way to increase the yield strength of the components using the ferrite-pearlite microstructure strengthened by precipitation hardening of VC. In this study, the influence of alloying elements, cooling rate and aging temperature on the precipitation hardening behavior of V containing middle carbon steels was investigated. The precipitation hardening is very sensitive to cooling rate and aging temperature. The addition of Si reduced the sensitivity of the cooling rate. The deformation in the austenite region slightly decreases the precipitation hardening. From a detailed analysis, it was found out that the precipitation hardening is strongly influenced by the γ→α transformation behavior, which indicates that the interphase precipitation plays a significant role for the precipitation hardening.

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13

Murakami, Masahiro, Nobuo Nakada, Toshihiro Tsuchiyama, Setsuo Takaki y Yoshitaka Adachi. "Multiple Precipitation Behavior of Niobium Carbide and Copper in Martensitic Steel". Advanced Materials Research 89-91 (enero de 2010): 395–99. http://dx.doi.org/10.4028/www.scientific.net/amr.89-91.395.

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The multiple precipitation behavior of NbC and Cu particles in martensitic structure was investigated by using 0.05C-0.46Nb-2Cu-1.5Mn steel (NbC-Cu steel). Additionally, 0.05C-0.45Nb-2Mn steel (NbC steel) and 2Cu-5Mn steel (Cu steel) were also prepared to examine the respective precipitation behaviors of NbC and Cu. Aging treatment at 873K after quenching revealed that these steels exhibit typical age hardening. Comparing the NbC steel and Cu steel in the precipitation rate, the Cu precipitated much faster than the NbC. On the other hand, the peak hardness in NbC-Cu steel is higher than that by the respective precipitations in NbC steel and Cu steel. Besides, the aging time for the peak hardness in NbC-Cu steel was between those in NbC steel and Cu steel. This suggests that the NbC and Cu particles were separately precipitated within martensite matrix and each of them contributed to the hardening in NbC-Cu steel. As a result of TEM investigation for crystallographic characteristics of the precipitates, the NbC and Cu particles had different crystallographic orientation relationship with tempered martensite matrix: Baker-Nutting relationship for NbC particle and Kurdjumov-Sachs relationship for Cu particle.

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14

Kirsten, Tina, Fatih Bülbül, Marcel Wicke, Hans-Jürgen Christ, Angelika Brückner-Foit y Martina Zimmermann. "Influence of microstructural discontinuities on the behaviour of long cracks in the VHCF regime for the aluminium alloys EN AW 6082 and EN AW 5083". MATEC Web of Conferences 165 (2018): 20005. http://dx.doi.org/10.1051/matecconf/2018165020005.

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In the present study two different aluminium alloys, the precipitation hardening alloy EN AW 6082 (peak-aged and overaged) and the work-hardening alloy EN AW 5083 (soft annealed) were examined. Fatigue cracks were initiated by means of a focused ion beam notch and a longdistance microscope was used for in-situ observation of the crack growth behaviour. The crack growth was investigated at constant stress intensity factors near the threshold regime. During the insitu investigation a change in crack growth velocity was detected. It could be observed that the barrier function of grain boundaries and primary precipitations are the major reason for crack growth retardation despite the fact that the crack is in the long crack growth range. The microstructural influence becomes more important with decreasing ΔK values, meanwhile the average crack growth rate decreases simultaneously. Experimental results have shown that the Febased precipitates are influencing the crack growth rate for both aluminium alloys. Meanwhile, grain boundaries are causing a deceleration of the crack growth rate primarily in case of the work hardened aluminium alloy. This is assumed to be the reason for the smaller average crack growth rate in EN AW 5083 compared to that observed for the precipitation hardening alloy while applying comparable ΔK values.

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15

Kirsten, Tina, Fatih Bülbül, Marcel Wicke, Hans-Jürgen Christ, Angelika Brückner-Foit y Martina Zimmermann. "Influence of microstructural discontinuities on the behaviour of long cracks in the VHCF regime for the aluminium alloys EN AW 6082 and EN AW 5083". MATEC Web of Conferences 165 (2018): 20005. http://dx.doi.org/10.1051/matecconf/201816520005.

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In the present study two different aluminium alloys, the precipitation hardening alloy EN AW 6082 (peak-aged and overaged) and the work-hardening alloy EN AW 5083 (soft annealed) were examined. Fatigue cracks were initiated by means of a focused ion beam notch and a longdistance microscope was used for in-situ observation of the crack growth behaviour. The crack growth was investigated at constant stress intensity factors near the threshold regime. During the insitu investigation a change in crack growth velocity was detected. It could be observed that the barrier function of grain boundaries and primary precipitations are the major reason for crack growth retardation despite the fact that the crack is in the long crack growth range. The microstructural influence becomes more important with decreasing ΔK values, meanwhile the average crack growth rate decreases simultaneously. Experimental results have shown that the Febased precipitates are influencing the crack growth rate for both aluminium alloys. Meanwhile, grain boundaries are causing a deceleration of the crack growth rate primarily in case of the work hardened aluminium alloy. This is assumed to be the reason for the smaller average crack growth rate in EN AW 5083 compared to that observed for the precipitation hardening alloy while applying comparable ΔK values.

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16

Sun, Shaoheng, Zhiyong Xue, Licong An, Xiaohua Chen y Yifei Liu. "A Novel Design to Enhance the Mechanical Properties in Cu-Bearing Antibacterial Stainless Steel". Materials 13, n.º 2 (15 de enero de 2020): 403. http://dx.doi.org/10.3390/ma13020403.

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A novel method based on nano-scale precipitation hardening has been studied to strengthen copper-bearing ferrite antibacterial stainless steel. Bimodal precipitations can be observed after antibacterial annealing and low temperature aging treatment, which are large rod-shaped precipitates and nano-sized spherical precipitates, respectively. Due to two different morphological precipitates, the strength of the material is significantly improved without sacrificing formability, and at the same time, the excellent antibacterial properties remain. Under low temperature aging treatment, there is no obvious evidence to show the segregation at the interface between the rod-shaped copper precipitation and the matrix due to the low segregation coefficient of copper. The nano-sized copper precipitation uniformly nucleated and distributed on the matrix. The optimized heat treatment process is antibacterial annealing at 800 °C for half an hour followed by one-hour-aging treatment at 550 °C.

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17

Miao, W. F. y D. E. Laughlin. "Precipitation hardening in aluminum alloy 6022". Scripta Materialia 40, n.º 7 (marzo de 1999): 873–78. http://dx.doi.org/10.1016/s1359-6462(99)00046-9.

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18

Nie, Jian-Feng. "Precipitation and Hardening in Magnesium Alloys". Metallurgical and Materials Transactions A 43, n.º 11 (21 de julio de 2012): 3891–939. http://dx.doi.org/10.1007/s11661-012-1217-2.

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19

Camurri, Carlos, Claudia Carrasco, Antonio Pagliero y Rafael Colás. "Optimal Precipitation Hardening Conditions in Lead Base Anodes for Copper Electrowinning". Materials Science Forum 638-642 (enero de 2010): 1091–97. http://dx.doi.org/10.4028/www.scientific.net/msf.638-642.1091.

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The suitable yield stress of Pb-0.07%Ca-1.3%Sn anodes of 6 mm thickness for copper electrowinning is achieved by means of deformation and precipitation hardening processes, being its useful life dependant of this yield stress. In such sense the objective of the present work is to optimize the precipitation hardening, finding for this purpose the best cooling conditions of the anodes in the molds and of the hot rolling temperature. The results show that increasing cooling rate of ingots from natural cooling the precipitation hardening is enhanced, with increases of 10% and 12.5 % on the yield stress and working life of the anodes respectively, and that a minimum of 45 days of ageing is necessary to reach stable conditions for the precipitation hardening, with precipitates formation as CaSn3. The hot roll temperature as not significant effect on the precipitation hardening of the anodes.

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20

Senuma, Takehide, Masanori Sakamoto y Yoshito Takemoto. "Precipitation and Precipitation Hardening Behavior of V and/or Cu Bearing Middle Carbon Steels". Materials Science Forum 638-642 (enero de 2010): 3491–95. http://dx.doi.org/10.4028/www.scientific.net/msf.638-642.3491.

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In this study, the precipitation and precipitation hardening behavior of a 0.3%V and 2%Cu bearing middle carbon steel has been investigated in comparison with that of a 0.3%V bearing steel and a 2%Cu bearing steel. The precipitation treatment was carried out isothermally at 600°C.The amount of the precipitation hardening of the 0.3%V and 2%Cu bearing steel is nearly equal to the sum of the precipitation hardening of the 0.3%V bearing steel and the 2%Cu bearing steel In the 0.3%V bearing steel, precipitates were observed in rows, which indicates the occurrence of the interphase precipitation while precipitates observed in the 2%Cu bearing steel were randomly dispersed. In the V and Cu bearing steel, randomly dispersed precipitates were not observed where there were aligned precipitates. In the paper, the different precipitation behavior of the three steels is discussed.

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21

Frandsen, Rasmus B., Thomas Christiansen y Marcel A. J. Somers. "Simultaneous surface engineering and bulk hardening of precipitation hardening stainless steel". Surface and Coatings Technology 200, n.º 16-17 (abril de 2006): 5160–69. http://dx.doi.org/10.1016/j.surfcoat.2005.04.038.

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22

Deschamps, A., S. Esmaeili, W. J. Poole y M. Militzer. "Strain hardening rate in relation to microstructure in precipitation hardening materials". Le Journal de Physique IV 10, PR6 (abril de 2000): Pr6–151—Pr6–156. http://dx.doi.org/10.1051/jp4:2000626.

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23

V, Vembu y Ganesan G. "Effect of Precipitation Hardening on Tensile, Fatigue and Fracture Toughness Behaviour of 8011 Al/ 15%SiCp Metal Matrix Composite". Bonfring International Journal of Industrial Engineering and Management Science 9, n.º 3 (30 de septiembre de 2019): 01–06. http://dx.doi.org/10.9756/bijiems.9030.

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24

Pázmán, Judit, Zoltán Gácsi y György Krállics. "Comparative Study of Precipitation Hardened and Equal Channel Angular Pressed Powder Metallurgical Al-Alloy Samples". Materials Science Forum 752 (marzo de 2013): 20–29. http://dx.doi.org/10.4028/www.scientific.net/msf.752.20.

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In the research work the precipitation hardening and/or equal channel angular pressing (ECAP) of PM aluminium alloy (AlCuSiMg) samples were investigated. The aim of the research was to determine the optimal parameters for precipitation hardening, especially temperature and time (in terms of maximal strength), and to test the ECAP pressing number for the same properties of precipitation hardened samples. The samples produced were studied by SEM, X-ray diffraction. The results showed that the PM samples had higher mechanical properties after one pressing by ECAP than after precipitation hardening with optimal parameters. In severe plastic deformation a heated die with a channel angle of 90° and ‘A’ route was used. During the heat treatment the applied temperature of the solution treatment was 420-540°C for 1 hour or 3 hours, and hardening was applied at 180°C for 5 hours.

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25

FURUKAWA, Minoru, Hai-bo WANG y Minoru NEMOTO. "Precipitation hardening of Al-0.5%Zr alloy." Journal of Japan Institute of Light Metals 40, n.º 1 (1990): 20–26. http://dx.doi.org/10.2464/jilm.40.20.

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26

Senda, Tetsuya, Kazuyoshi Matsuoka, Shinya Hayashi, Chiori Takahashi, Noriyuki Kotani, Shigeru Kitamura, Iwao Watanabe, Takahiro Majima y Isamu Nishimori. "Brittle Fracture of Precipitation Hardening Stainless Steel". JOURNAL OF THE MARINE ENGINEERING SOCIETY IN JAPAN 33, n.º 10 (1998): 764–71. http://dx.doi.org/10.5988/jime1966.33.764.

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27

Souza, Pedro Henrique Lamarão, Carlos Augusto Silva de Oliveira y José Maria do Vale Quaresma. "Precipitation hardening in dilute Al–Zr alloys". Journal of Materials Research and Technology 7, n.º 1 (enero de 2018): 66–72. http://dx.doi.org/10.1016/j.jmrt.2017.05.006.

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28

Vourlias, G., N. Pistofidis y K. Chrissafis. "High-temperature oxidation of precipitation hardening steel". Thermochimica Acta 478, n.º 1-2 (noviembre de 2008): 28–33. http://dx.doi.org/10.1016/j.tca.2008.08.006.

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29

Nie, J. F. y B. C. Muddle. "Precipitation hardening of Mg-Ca(-Zn) alloys". Scripta Materialia 37, n.º 10 (noviembre de 1997): 1475–81. http://dx.doi.org/10.1016/s1359-6462(97)00294-7.

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30

Mitlin, D., U. Dahmen, V. Radmilovic y J. W. Morris. "Precipitation and hardening in Al–Si–Ge". Materials Science and Engineering: A 301, n.º 2 (marzo de 2001): 231–36. http://dx.doi.org/10.1016/s0921-5093(00)01799-8.

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31

Markandeya, R., S. Nagarjuna y D. S. Sarma. "Precipitation hardening of Cu–Ti–Cr alloys". Materials Science and Engineering: A 371, n.º 1-2 (abril de 2004): 291–305. http://dx.doi.org/10.1016/j.msea.2003.12.002.

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32

Elgallad, E. M., J. Lai y X.-G. Chen. "Precipitation hardening of AA2195 DC cast alloy". Canadian Metallurgical Quarterly 53, n.º 4 (13 de julio de 2014): 494–502. http://dx.doi.org/10.1179/1879139514y.0000000149.

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33

Markandeya, R., S. Nagarjuna y D. S. Sarma. "Precipitation hardening of Cu-4Ti-1Cd alloy". Journal of Materials Science 39, n.º 5 (marzo de 2004): 1579–87. http://dx.doi.org/10.1023/b:jmsc.0000016155.64776.52.

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34

Markandeya, R., S. Nagarjuna y D. S. Sarma. "Precipitation hardening of Cu – Ti – Zr alloys". Materials Science and Technology 20, n.º 7 (julio de 2004): 849–58. http://dx.doi.org/10.1179/026708304225017409.

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35

Bamberger, M., G. Levi y J. B. Vander Sande. "Precipitation hardening in Mg-Ca-Zn alloys". Metallurgical and Materials Transactions A 37, n.º 2 (febrero de 2006): 481–87. http://dx.doi.org/10.1007/s11661-006-0019-9.

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36

Markandeya, R., S. Nagarjuna y D. S. Sarma. "Precipitation Hardening of Cu-3Ti-1Cd Alloy". Journal of Materials Engineering and Performance 16, n.º 5 (15 de mayo de 2007): 640–46. http://dx.doi.org/10.1007/s11665-007-9082-7.

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37

Ogorodnikova, O. M. y E. V. Maksimova. "Precipitation Hardening of Castable Iron-Nickel Invars". Metal Science and Heat Treatment 57, n.º 3-4 (julio de 2015): 143–45. http://dx.doi.org/10.1007/s11041-015-9852-z.

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38

Viswanathan, U. K., G. K. Dey y M. K. Asundi. "Precipitation hardening in 350 grade maraging steel". Metallurgical Transactions A 24, n.º 11 (noviembre de 1993): 2429–42. http://dx.doi.org/10.1007/bf02646522.

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39

Hornbogen, E., A. K. Mukhopadhyay y E. A. Starke. "Precipitation hardening of Al-(Si, Ge) alloys". Scripta Metallurgica et Materialia 27, n.º 6 (septiembre de 1992): 733–38. http://dx.doi.org/10.1016/0956-716x(92)90497-3.

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40

Arensburger, D. S. y S. M. Letunovich. "Properties of sintered precipitation-hardening copper alloys". Soviet Powder Metallurgy and Metal Ceramics 25, n.º 7 (julio de 1986): 553–56. http://dx.doi.org/10.1007/bf00792358.

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41

Wang, D., H. Kahn, F. Ernst y A. H. Heuer. "NiAl precipitation in delta ferrite grains of 17-7 precipitation-hardening stainless steel during low-temperature interstitial hardening". Scripta Materialia 108 (noviembre de 2015): 136–40. http://dx.doi.org/10.1016/j.scriptamat.2015.07.001.

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42

Saikawa, Seiji, Yuhei Ebata, Kiyoshi Terayama, Susumu Ikeno y Emi Yanagihara. "Age-Hardening Behavior of Mg-Al-Zn Alloys Produced by Sand Mold Casting". Materials Science Forum 783-786 (mayo de 2014): 467–71. http://dx.doi.org/10.4028/www.scientific.net/msf.783-786.467.

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In recent years, Mg-Al-Zn system alloy has been used for the parts in the automobile for weight reductions. The age-hardening behavior of Mg-6mass%Al (-1mass%Zn)-0.3mass%Mn alloys sand mold castings were investigated by Vickers hardness measurement and optical microscopic observation. Both alloys were solution-treated and then isothermal-aged at 473, 498 and 523K. For each aging temperature, both alloys were indicated age-hardening obviously, and decreased the value of maximum hardness and shorten time to maximum hardness with heighten aging temperature. Age-hardening curves for both alloys approximately showed the same change of hardness. However, these optical micrographs after aging treatment are observed different microstructure. In case of AM60 magnesium alloy, discontinuous precipitation preferentially occurred in aged sample. The volume fraction of discontinuous precipitation was larger than that of continuous precipitation. On the other hand, in case of AZ61 magnesium alloy, the volume fraction of continuous precipitation was larger than that of discontinuous precipitation. Furthermore, over-aged sample of both alloys were consisted of discontinuous precipitation, continuous precipitation and pre-precipitation area.

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43

Hirosawa, Shoichi, Yong Peng Tang, Zenji Horita, Seung Won Lee, Kenji Matsuda y Daisuke Terada. "Three Strategies to Achieve Concurrent Strengthening by Ultrafine-Grained and Precipitation Hardenings for Severely Deformed Age-Hardnable Aluminum Alloys". Advanced Materials Research 1135 (enero de 2016): 161–66. http://dx.doi.org/10.4028/www.scientific.net/amr.1135.161.

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In this paper, comprehensive studies on the age-hardening behavior and precipitate microstructures of severely deformed and then artificially aged aluminum alloys have been conducted to clarify whether or not concurrent strengthening by ultrafine-grained and precipitation hardenings can be achieved. From our graphically-illustrated equivalent strain dependence of both the attained hardness and increment/decrement in hardness during aging (i.e. age-hardenability), three strategies to maximize the combined processing of severe plastic deformation and age-hardening technique are proposed. (1) Lowering of aging temperature and (2) utilization of microalloying elements can improve not only the attained hardness but also the age-hardenability of high-pressure torsion (HPT) specimens of Al-Mg-Si (-Cu) alloy due to the increased volume fraction of transgranular precipitates. A further increase in hardness can be achieved by (3) taking advantage of spinodal decomposition for HPTed Al-Li-Cu alloy, in which nanoscale precipitates of δ’ phase are successfully formed within ultrafine grains, irrespective of the higher number density of grain boundaries. The attained hardness of >HV290 in the latter alloy is almost the highest among conventional wrought aluminum alloys, and therefore our proposed strategies will be useful for designing concurrently strengthened severely-deformed age-hardenable aluminum alloys.

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44

Ferrante, Maurizio. "A Short Summary of Present Knowledge and some Experimental Observations on the Ductility of Sub-Microcrystalline Aluminium Alloys". Materials Science Forum 633-634 (noviembre de 2009): 179–96. http://dx.doi.org/10.4028/www.scientific.net/msf.633-634.179.

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It is well known that the low ductility of nanostructured materials seriously impairs their commercial development. In its turn that mechanical property is associated to the work-hardening behaviour and the vast literature on this relationship is a measure of its importance. This paper presents a short review of the basic models of work-hardening, dealing initially with conventional “coarse” grain metals and alloys, then moving to the behaviour of sub-microcrystalline materials within the bounds of Al alloys and Equal Channel Angular Pressing. Finally, the interrelations of tensile properties, work-hardening behaviour and microstructure are illustrated by data obtained on a precipitation and a non-precipitation hardening Al alloys, namely Al-4%Cu and AA3004. Results show that low temperature aging results in higher strength and high work hardening rate, besides high ductility. The effects of precipitation and of annealing heat treatments are discussed.

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45

Chen, Lei, Ren Bo Song, Fu Qiang Yang y Yu Pei. "Working Hardening Mechanism and Aging Treatment Behaviors of D631 Precipitation Hardening Stainless Steel Wire". Materials Science Forum 788 (abril de 2014): 362–66. http://dx.doi.org/10.4028/www.scientific.net/msf.788.362.

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Precipitation hardening stainless steel has the advantages of both austenitic stainless steel and martensitic stainless steel, including good corrosion resistance, excellent processability and high strength. With the evolution of microstructure and properties of semi-austenitic precipitation hardening stainless steel (D631) during drawing process and aging treatment, the working hardening behaviors, law of phase transition, dissolution and precipitation state of alloying element are investigated to gain the toughness mechanism of D631. The results show that the tensile strength increases with the increase of the reduction of area, on the contrary, the plasticity decreases gradually. The tensile strength is 1529 MPa while the reduction of area is 54%. By means of X-ray diffraction (XRD) and metallograpic observation, the content of martensite increases with the increase of deformation, and makes the higher strength and lower plasticity. The alloying element dissolved in the matrix precipitates in fine particles by aging treatment, resulting in a higher strength of 1948MPa.

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46

Huo, Xiang Dong, Lin Guo, Jin Song Feng, Chao Luo y Jun Qu. "Development of Hot Rolled Ship Plate with High Strength and High Toughness". Advanced Materials Research 690-693 (mayo de 2013): 106–9. http://dx.doi.org/10.4028/www.scientific.net/amr.690-693.106.

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A new hot-rolled ship plate with high strength and high toughness is successfully developed through chemical composition design and TMCP process. Experimental methods, such as OM, TEM and X-EDS, were used to study the microstructure and precipitates of steel. The primary microstructural constituent is acicular ferrite, quasi-polygonal ferrite with second constituents along grain boundaries. Lath width of acicular ferrite is about 1μm. Cubic particles about several hundreds nanometers and nanometer particles exist in experimental steel. It can be concluded that acicular ferrite is the main reason for high strength and super toughness. precipitation hardening due to dispersed precipitations of carbonitrides can not be overlooked.

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47

Dutta, R. S., A. Sarkar, B. Vishwanadh, R. Tewari, P. U. Sastry y G. K. Dey. "Precipitation-hardening of superalloy 693 and modeling of initial stages of hardening". Materials Characterization 138 (abril de 2018): 127–35. http://dx.doi.org/10.1016/j.matchar.2018.02.007.

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48

Starink, Marco J. y J. L. Yan. "Precipitation Hardening in Al-Cu-Mg Alloys: Analysis of Precipitates, Modelling of Kinetics, Strength Predictions". Materials Science Forum 519-521 (julio de 2006): 251–58. http://dx.doi.org/10.4028/www.scientific.net/msf.519-521.251.

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In Al-Cu-Mg with compositions in the α+S phase field, precipitation hardening is a twostage process. Experimental evidence shows that the main precipitation sequence in alloys with Cu contents in excess of 1wt% is involves Cu-Mg co-clusters, GPBII/S'' and S. The first stage of the age hardening is due to the formation of Cu-Mg co-clusters, and the hardening can be modelled well by a modulus hardening mechanism. The appearance of the orthorhombic GPBII/S'' does not influence the hardness. The second stage of the hardening is due to the precipitation of S phase, which strengthens the alloy predominantly through the Orowan looping mechanism. These findings are incorporated into a multi-phase, multi mechanism model for yield strength of Al-Cu-Mg based alloys. The model is applied to a range of alloys with Cu:Mg ratios between 0.1 and 1 and to heat treatments ranging from room temperature ageing and artificial isothermal ageing to rapid heating to the solution treatment temperature. The predictive capabilities of this model are reviewed and its constitutive components are compared and contrasted with a range of other methods, such as the Kampmann-Wagner and JMAK models for precipitation as well as the LSW model for coarsening.

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49

Qin, Jian, Zhan Zhang y X.-Grant Chen. "Mechanical properties and thermal stability of hot-rolled Al–15%B4C composite sheets containing Sc and Zr at elevated temperature". Journal of Composite Materials 51, n.º 18 (13 de octubre de 2016): 2643–53. http://dx.doi.org/10.1177/0021998316674351.

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The microstructure, mechanical properties, thermal stability and tensile fracture of two hot-rolled Al-15 vol.% B4C composite sheets (S40 with 0.4 wt.% Sc and SZ40 with 0.4 wt.% Sc and 0.24 wt.% Zr) were investigated. During multi-pass hot rolling, coarse Al3Sc or Al3(Sc, Zr) precipitations appeared and resulted in the loss of most of their hardening effect. In an appropriate post-rolling heat treatment, the hot-rolled sheets regained a significant precipitation hardening because of the precipitation of fine nanoscale Al3Sc and Al3(Sc,Zr) that uniformly distributed in the aluminum matrix. After the peak aging, the ultimate tensile strength at ambient temperature of the S40 and SZ40 sheets can reach 198 MPa and 215 MPa, respectively. During 2000 h of annealing at 300℃, the strengths at ambient temperature of both S40 and SZ40 composite sheets slowly decreased with increasing annealing time. However, the tensile strengths at 300℃ of both S40 and SZ40 composite sheets remained nearly unchanged and were less sensitive to the annealing time and more tolerable for precipitate coarsening, which demonstrated an excellent long-term thermal stability of both materials at elevated temperature. The tensile fracture at ambient temperature of both S40 and SZ40 composite sheets was dominated by the brittle B4C particle fracture, whereas the interfacial decohesion of B4C particles became the prominent characteristic of the fracture at 300℃.

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50

Na, Shun Sang, Jian Sha Chen, Chao Fu, Guo Tao Zhang y Qian Xu. "Study on the Law of Phrase Transformation of High-Carbon Matrix Steel 4Cr-3Mo-3V-2W". Advanced Materials Research 284-286 (julio de 2011): 1610–14. http://dx.doi.org/10.4028/www.scientific.net/amr.284-286.1610.

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The study on the phase transformation law of High-Carbon Matrix steel 4Cr-3Mo-3V-2W-Ni-Nb, which is processed in different heat treatment, is conducted by means of metallographic observation, hardness determination and phase analysis conducted with the help of X-ray diffraction. The results indicate what is as follow: through quenching at 970°C, the main precipitations of alloy carbide are V4WC5, Cr7C3 and Fe3W3C at 200~300°C, V4WC5 and Cr7C3 at 400°C, V4WC5 and Cr7C3 at 500°C, V4WC5, Cr7C3 and Mn23C6 at 600°C. The transformation of residual austenite is thorough completed above 400 °C and the cause of secondary hardening is the precipitation of V4WC5 and V4C2.67.

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