Passage
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stringlengths 25
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stringlengths 6
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Supercooling investigation and critical cooling rate for glass formation in Pd–Cu–Ni–P alloy. 1 When nucleating homogeneously, R c is evaluated to be 2.08×10^(-5) K/s under continuous cooling.
|
10.1016/S1359-6454(99)00030-0
|
Cu30Ni10P20Pd40
| 0.000021
|
K/s
| -4.681937
|
Prediction of the glass forming ability in Cu–Zr binary and Cu–Zr–Ti ternary alloys. In their study, the associated solution model was adopted for describing the effect of short range ordering in the undercooled liquid. Although the thermodynamic data at low temperature were properly taken into account, there is some discrepancy between the calculated and experimental results, e.g. the cooling rate of Cu–50at.%% Zr alloy is only 10^(-4) K/s, which is much slower critical cooling than the reported data.
|
10.1016/j.intermet.2007.07.008
|
Cu0.5Zr0.5
| 0.0001
|
K/s
| -4
|
First principles modeling of the structural, electronic, and vibrational properties of Ni40Pd40P20 bulk metallic glass. The study indicates that a value of T rg close to 2/3 was achieved in their experiments. In a later work, He et al. [14] produced Ni40Pd40P20 BMG using a critical cooling rate of 10^(-3) K/s.
|
10.1016/j.nocx.2018.100004
|
Ni40P20Pd40
| 0.001
|
K/s
| -3
|
Thermodynamics, kinetics, and crystallization of Pt57.3Cu14.6Ni5.3P22.8 bulk metallic glass. These alloys show an extraordinary ability to resist crystallization and may solidify as a glass when cooled at sufficient rates. One of the best metallic glass formers yet discovered is the Pd43Cu27Ni10P20 alloy, which under certain processing conditions has demonstrated a remarkably low critical cooling rate for glass formation of 0.005K/s [1], resulting in a critical casting thickness of >72mm [2].
|
10.1016/j.actamat.2006.09.024
|
Cu27Ni10P20Pd43
| 0.005
|
K/s
| -2.30103
|
On the new criterion to assess the glass-forming ability of metallic alloys. As shown in Fig. 4(l) and Table 3, a rather high correlation coefficient (R ^(2) =0.922) indicates that Eq. (22) fits the experimental data points very well. For example, Eq. (22) predicts the critical cooling rate R c ω for Pd43.2Ni8.8Cu28P20 bulk metallic glass is 6.50×10^(-3) K/s, which is good agreement with the experimentally measured R c (i.e., 9×10^(-3) K/s for this alloy, see Table 2).
|
10.1016/j.msea.2009.01.063
|
Cu28Ni8.8P20Pd43.2
| 0.0065
|
K/s
| -2.187087
|
On the new criterion to assess the glass-forming ability of metallic alloys. As shown in Fig. 4(l) and Table 3, a rather high correlation coefficient (R ^(2) =0.922) indicates that Eq. (22) fits the experimental data points very well. For example, Eq. (22) predicts the critical cooling rate R c ω for Pd43.2Ni8.8Cu28P20 bulk metallic glass is 6.50×10^(-3) K/s, which is good agreement with the experimentally measured R c (i.e., 9×10^(-3) K/s for this alloy, see Table 2).
|
10.1016/j.msea.2009.01.063
|
Cu28Ni8.8P20Pd43.2
| 0.009
|
K/s
| -2.045757
|
Thermodynamics, enthalpy relaxation and fragility of the bulk metallic glass-forming liquid Pd43Ni10Cu27P20. These findings provide the possibility to experimentally measure the thermodynamic properties in bulk metallic glasses [2,12,13]. So far, the Pd43Ni10Cu27P20 alloy shows the best glass-forming ability with a critical cooling rate as low as 0.01 K/s [14].
|
10.1016/j.actamat.2003.10.003
|
Cu27Ni10P20Pd43
| 0.01
|
K/s
| -2
|
High temperature homogeneous plastic flow behavior of a Zr based bulk metallic glass matrix composite. So, the mechanism of the high temperature deformation of BMG composites needs to be further investigated. Among the multi-component BMGs, the Zr41.2Ti13.8Cu12.5Ni10Be22.5 alloy (Vitreloy 1) is a particularly good glass former with a critical cooling rate as low as approximately 1K/min [27].
|
10.1016/j.jallcom.2010.02.017
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 0.016667
|
K/s
| -1.778151
|
Air-oxidation of a Pd40Ni40P20 bulk glassy alloy at 250–420°C. In addition, this glassy alloy had a larger ΔT x value of ∼72°C, which offered a better welding ability and superplasticity (up to a 1260% deformation) [9]. Besides, it was reported that the quaternary version of this family, the Pd43Cu27Ni10P20 bulk-metallic glass (Pd4-BMG), could retain its amorphous structure in a relative lower critical cooling rate (∼4°C/min), as compared to that of the ternary alloy (∼60°C/min) [10].
|
10.1016/j.jallcom.2013.01.175
|
Cu27Ni10P20Pd43
| 0.066667
|
K/s
| -1.176091
|
Electronic structure of Pd42.5Ni7.5Cu30P20, an excellent bulk metallic glass former: Comparison to the Pd40Ni40P20 reference glass. Bulk metallic glasses of Pd–Ni–Cu–P alloys, discovered by Nishiyama and Inoue [1], have been intensively investigated due to their good glass-forming abilities (GFA). They have optimized the concentration dependence of the critical cooling rate and found that Pd42.5Ni7.5Cu30P20 has at present the slowest critical cooling rate – 0.067K/s – and can form a massive bulk glass with a diameter of >40mm by simple water-quenching [2].
|
10.1016/j.actamat.2007.01.041
|
Cu30Ni7.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
Soft X-ray emission study of Pd–Ni–Cu–P bulk metallic glass. Bulk metallic glasses of Pd–Ni–Cu–P alloys, discovered by Nishiyama and Inoue [1], have intensively been investigated due to their good glass-forming abilities (GFA). They have optimized the concentration dependence of the critical-cooling-rate, and found that Pd42.5Ni7.5Cu30P20 has at present the slowest critical-cooling-rate of 0.067K/s and can form a massive bulk glass with a diameter of more than 40mm by simple water-quenching [2].
|
10.1016/j.elspec.2006.12.061
|
Cu30Ni7.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
Isothermal crystallization kinetics analysis of melt-spun Pd42.5Cu30Ni7.5P20 amorphous ribbons. A lot of researches about the nucleation and crystallization process have been performed with this glassy system [4–10]. Recently Pd42.5Cu30Ni7.5P20 has been reported as a eutectic composition with the lowest critical cooling rate for glass formation of 0.067K/s and its stability and nucleation behavior has been discussed [11].
|
10.1016/j.jallcom.2004.09.019
|
Cu30Ni7.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
Synthesis and mechanical properties of an amorphous Zr–Ni–Al–Cu alloy. Inoue [5] succeeded in finding new multicomponent alloy systems, especially Zr-based alloys, produced with lower critical cooling rates 0.1–10K/s. The lowest critical cooling rate (R c) for the formation of a glassy phase has been reported as low as 0.067K/s for Pd42.5Cu30Ni17.5P20 alloy [6].
|
10.1016/j.jallcom.2005.12.008
|
Cu30Ni17.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
The effects of Si substitution on the glass forming ability of Ni–Pd–P system, a DFT study on crystalline related clusters. Inoue and coworkers had found new multicomponent BMGs with excellent glass-formation ability (GFA) [7], for example: Mg-, Ln–Zr-, Fe-, Pd–Cu-, Pd–Fe-, Ti- and Ni-based alloy systems. In this context, Pd40Ni10CuCuP20 and Pd42.5Ni7.5Cu30P20 have the lowest critical cooling rate of 0.10 and 0.067K/s, which can be associated to the best GFA [8,9].
|
10.1016/j.jnoncrysol.2014.01.001
|
Cu30Ni7.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
Detailed structural analysis of amorphous Pd40Cu40P20: Comparison with the metallic glass Pd40Ni40P20 from the viewpoint of glass forming ability. This finding indicates a large size arrangement of Ni atoms, which may set the expectations for the excellent GFA of PNP beyond the original PH article [25]. To confirm such structure-property relationships, a further systematic work is necessary on partial structures of a Pd 42.5 Ni 7.5 Cu 30 P20 (PNCP) bulk metallic glass, which is mostly the mixture of PNP and PCP, and shows a champion critical cooling rate of 0.067 K/s at present forming a massive bulk glass with a diameter of more than 40 mm [38].
|
10.1016/j.jnoncrysol.2020.120536
|
Cu30Ni7.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
Simultaneous and different nucleation modes in undercooled Pd–Cu–Ni–P melts. The conventional PCNP-0 and the similar Pd43Cu27Ni10P20 alloy appear to show a slightly off-eutectic composition. More recently, we have found that a new Pd42.5Cu30Ni7.5P20 alloy (PCNP-7) has the lowest R c of 0.067K/s [13].
|
10.1016/j.msea.2003.10.146
|
Cu30Ni7.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
Brazing of Cu with Pd-based metallic glass filler. Bulk metallic glass is ordinarily fabricated from a molten base alloy by the melt spinning method or casting method. Some types of metallic glass, such as Mg- [1], Zr- [2,3], Fe- [4,5], Pd- [6] and Ni-based [7] alloys, have a low critical cooling rate, R c. Especially, Pd42.5Cu30Ni7.5P20 has an R c of 0.067K/s [8].
|
10.1016/j.mseb.2007.09.084
|
Cu30Ni7.5P20Pd42.5
| 0.067
|
K/s
| -1.173925
|
Metallic glasses…on the threshold. At present the largest diameter cast into a fully glassy state appears to be 72 mm ^(6) . As the critical cooling rate for glass formation for the alloy in question, Pd40Cu30Ni10P20, can be markedly decreased ^(7) by fluxing treatments to be 0.067 K s^(-1), it is likely that 72 mm is far from any fundamental limit.
|
10.1016/S1369-7021(09)70037-9
|
Cu30Ni10P20Pd40
| 0.067
|
K/s
| -1.173925
|
Simultaneous and different nucleation modes in undercooled Pd–Cu–Ni–P melts. Since the first report of the Pd40Cu30Ni10P20 (PCNP-0) alloy with a low critical cooling rate for glass formation (R c) of 0.100K/s [1–6], several properties of the undercooled melt [7–10] were investigated due to its exceptional high thermal stability and retarded crystallization kinetics. Recently, Schroers et al. reported that a slightly lower R c of 0.09K/s was obtained for a similar Pd43Cu27Ni10P20 alloy [11].
|
10.1016/j.msea.2003.10.146
|
Cu27Ni10P20Pd43
| 0.09
|
K/s
| -1.045757
|
Design of new Zr–Al–Ni–Cu bulk metallic glasses. Many kinds of BMGs have been developed including Mg-, La-, Zr-, Ti-, Cu-, Nd-, Fe-, Pr-, Pd-, Ce-, Ca-, and other rare earth-based [7–12]. At present, the lowest critical cooling rate for BMG formation is as low as 0.10K/s for the Pd40Cu30Ni10P20 alloy and the maximum dimension with full amorphous state reaches values as large as about 10cm [13].
|
10.1016/j.jallcom.2008.01.016
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Glass forming ability and thermal stability of Ni63Cu9Fe8P20 melt spun ribbon. On the other hand, analysis of available binary and ternary phase diagrams containing Ni, Pd, Cu and P indicates that there are deep eutectics [11], which show a good glass forming ability, especially in compositions where one of the constituents is P. This feature in connection with sufficiently large difference of atomic diameters indicates that there is a chance to obtain the compositions with a large glass forming ability. This expectation is confirmed by the studies of Pd40Ni40P20 alloy [12,13] presenting the critical cooling rate as low as 0.16K/s as well as the Pd40Ni10Cu30P20 alloy [14] with the critical cooling rate of 0.1K/s.
|
10.1016/j.jnoncrysol.2004.07.055
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
The effects of Si substitution on the glass forming ability of Ni–Pd–P system, a DFT study on crystalline related clusters. Inoue and coworkers had found new multicomponent BMGs with excellent glass-formation ability (GFA) [7], for example: Mg-, Ln–Zr-, Fe-, Pd–Cu-, Pd–Fe-, Ti- and Ni-based alloy systems. In this context, Pd40Ni10CuCuP20 and Pd42.5Ni7.5Cu30P20 have the lowest critical cooling rate of 0.10 and 0.067K/s, which can be associated to the best GFA [8,9].
|
10.1016/j.jnoncrysol.2014.01.001
|
Cu2Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Simultaneous and different nucleation modes in undercooled Pd–Cu–Ni–P melts. Since the first report of the Pd40Cu30Ni10P20 (PCNP-0) alloy with a low critical cooling rate for glass formation (R c) of 0.100K/s [1–6], several properties of the undercooled melt [7–10] were investigated due to its exceptional high thermal stability and retarded crystallization kinetics. Recently, Schroers et al. reported that a slightly lower R c of 0.09K/s was obtained for a similar Pd43Cu27Ni10P20 alloy [11].
|
10.1016/j.msea.2003.10.146
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Parameters governing glass formation: A view from phase selection. For example, Pd40Cu30Ni10P20, as the best glass former known so far with critical cooling rate of 0.1K/s [34,35], has the lowest value of 214K, while the well-known non-glass forming alloy Ag–Cu has the highest (T e - T g) value of 732K, about 3.5 times that of for Pd40Cu30Ni10P20 (numbers indicates at: %, T g for Ag–Cu was approximated to be 0.25T m according to [36], where T m is the weighted melting point). However, the critical cooling rate for the latter is estimated to exceed 10^(10) K/s, much higher than that for the former.
|
10.1016/j.msea.2006.02.330
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Brazing of Cu with Pd-based metallic glass filler. These intermetallic compounds are brittle, so the mechanical strength of crystallized Pd40Cu30Ni10P20 alloy is less than that of the amorphous state. But, the results showed Pd40Cu30Ni10P20 filler could be joined to Cu in the amorphous state, since the metallic glass filler was quenched at the rate of 30K/s, which is faster than the critical cooling rate of the Pd40Cu30Ni10P20 filler (R c =0.1K/s).
|
10.1016/j.mseb.2007.09.084
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Bulk metallic glasses. The work of Inoue opened the door to the design of new families of BMGs [16] and attention was once again focussed on the investigation on BMG [11,16]. Many kinds of BMGs have been developed including MgCuY, LaAlNi, ZrAlNiCu, ZrAlNiCu(Ti, Nb), ZrTiCuNiBe, TiNiCuSn, CuZrTiNi, NdFeCoAl, LaAlNi, FeCoNiZrNbB, FeAlGaPCB, PrCuNiAl, PdNiCuP, etc. At present, the lowest critical cooling rate for BMG formation is as low as 0.10K/s for the Pd40Cu30Ni10P20 alloy and the maximum sample thickness reaches values as large as about 10cm [21].
|
10.1016/j.mser.2004.03.001
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Microstructures and properties of high-entropy alloys. Ternary, quaternary, or alloys with more constituent elements can form glasses in bulk forms at a slow cooling rate. Particularly, the GFA of certain multi-component alloys is close to that of the oxide glass; the critical cooling rate for the VIT-1 alloy is only 0.1Ks^(-1), and the critical size for glass formation reaches over 70mm in diameter [227].
|
10.1016/j.pmatsci.2013.10.001
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 0.1
|
K/s
| -1
|
Study of frequency dependence modulus of bulk amorphous alloys around the glass transition by dynamic mechanical analysis. In this study, we compare the frequency dependence of storage and loss moduli of two bulk amorphous alloys; Pd40Ni10Cu30P20 and La55Al25Cu10Ni5Co5. Pd40Ni10Cu30P20 amorphous alloy is one of the best metallic glass former known so far with a critical cooling rate of only 0.1 K/s sufficient to avoid crystallization and to obtain bulk metallic glass castings of up to 72 mm in diameter [3].
|
10.1016/S0966-9795(02)00143-7
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Supercooling investigation and critical cooling rate for glass formation in Pd–Cu–Ni–P alloy. Some other nucleation mechanisms, i.e. quenched-in nucleus or additional nucleation are also discussed. The previously obtained results of undercooling investigation in the Pd40Cu30Ni10P20 alloy[13]were re-analyzed in the present study, because the Pd40Cu30Ni10P20 alloy exhibits the lowest R c of 0.100K/s in the fluxed state.
|
10.1016/S1359-6454(99)00030-0
|
Cu30Ni10P20Pd40
| 0.1
|
K/s
| -1
|
Glass forming ability and thermal stability of Ni63Cu9Fe8P20 melt spun ribbon. On the other hand, analysis of available binary and ternary phase diagrams containing Ni, Pd, Cu and P indicates that there are deep eutectics [11], which show a good glass forming ability, especially in compositions where one of the constituents is P. This feature in connection with sufficiently large difference of atomic diameters indicates that there is a chance to obtain the compositions with a large glass forming ability. This expectation is confirmed by the studies of Pd40Ni40P20 alloy [12,13] presenting the critical cooling rate as low as 0.16K/s as well as the Pd40Ni10Cu30P20 alloy [14] with the critical cooling rate of 0.1K/s.
|
10.1016/j.jnoncrysol.2004.07.055
|
Ni40P20Pd40
| 0.16
|
K/s
| -0.79588
|
12 Functional bulk metallic glasses. Up until now, this glass is one of the best BMGs and represents the densest packing in zirconium-based compositions [21]. In 1997, Inoue and coworkers [12] obtained cylinders of diameter up to 75mm of Pd40Cu30Ni10P20 BMG at the critical cooling rate of 0.167Ks^(-1) using B2O3 flux treatment.
|
10.1016/B978-0-12-805056-9.00012-X
|
Cu30Ni10P20Pd40
| 0.167
|
K/s
| -0.777284
|
On the bulk glass formation in the ternary Pd-Ni-S system. From the technological point of view, one major motivation for the use of sulfur instead of phosphorous in glass forming systems is its better processability due to the existence of a stable liquid phase under ambient pressure and the absence of toxic modifications, simplifying the alloying process. Up to now, the ternary metallic alloy composition with the highest glass forming ability (GFA) is the near eutectic composition Pd40Ni40P20, showing a critical cooling rate as low as 0.17 K^(-1) [17–19], resulting in casting diameters of up to 25 mm [20].
|
10.1016/j.actamat.2018.07.039
|
Ni40P20Pd40
| 0.17
|
K/s
| -0.769551
|
Assessing continuous casting of precious bulk metallic glasses. The cooling rates, computed from the first derivatives of temperature with time, are comparable at approximately 15 K/s to 17 K/s. According to literature this is clearly higher than the critical cooling rate reported for Pd43Ni10Cu27P20 (0.2 K/s [22], after fluxing), but slightly lower than that documented for Pt57.3Cu14.6Ni5.3P22.8 (≈20 K/s [23,24], after fluxing).
|
10.1016/j.jnoncrysol.2018.09.035
|
Cu27Ni10P20Pd43
| 0.2
|
K/s
| -0.69897
|
Materials properties measurements and particle beam interactions studies using electrostatic levitation. The experiments were carried out with spherical, 2.5–3mm diameter, glass samples. The measured critical cooling rates leading to glass formation, for the processed LS and Pt-LS glasses, were 14±2°C/min and 130±5°C/min, respectively.
|
10.1016/j.mser.2013.12.001
|
Li2O6Si2
| 0.233333
|
K/s
| -0.632023
|
A new DTA method for measuring critical cooling rate for glass formation. The primary difference between the compositions was that VP2212 contained about 1.1wt% Al2O3, but VP2076 was alumina-free. In addition to the Li-disilicate melts, a 38Na2O–62SiO2 (mol%) glass with a known R c (∼19°C/min [7]) was also characterized.
|
10.1016/j.jnoncrysol.2005.03.029
|
Na76Si62O162
| 0.316667
|
K/s
| -0.499398
|
A new DTA method for measuring critical cooling rate for glass formation. The nose temperature (T n) and nose time (t n) as estimated from Fig. 12(a) and (b) are 775°C and 5min for the VP2212 melt, and 818°C and 2min for the VP2076 melt. Based on these results, R c for the VP2212 melt is ∼30°C/min, and ∼42°C/min for the VP2076 melt.
|
10.1016/j.jnoncrysol.2005.03.029
|
VP2212
| 0.5
|
K/s
| -0.30103
|
A new DTA method for measuring critical cooling rate for glass formation. For the 38Na2O–62SiO2, mol%, melt, analysis of Fig. 9 (and also Fig. 8(a)) predicts a critical cooling rate (R c) of 19±1°C/min. This is in excellent agreement with the value of 19°C/min determined for this composition by standard techniques [7], and this agreement strongly justifies the validity and usefulness of the newly developed method for measuring critical cooling rates for glass forming melts. The R c values for the VP2212 (Fig. 8(b)) and VP2076 (Fig. 8(c)) melts are 33±1°C/min and 41±2°C/min, respectively.
|
10.1016/j.jnoncrysol.2005.03.029
|
VP2212
| 0.55
|
K/s
| -0.259637
|
Prediction of the glass forming ability in Cu–Zr binary and Cu–Zr–Ti ternary alloys. For example, the fragility parameters for Cu64Zr26 and Cu60Zr32.5Ti7.5 alloys are 9.3 and 8.31, which are highest among the Cu–Zr binary and ternary alloys, respectively. These two alloys also have the lowest critical cooling rate of 4.32×10^(2) K/s and 0.64K/s.
|
10.1016/j.intermet.2007.07.008
|
Cu60Ti7.5Zr32.5
| 0.64
|
K/s
| -0.19382
|
A new DTA method for measuring critical cooling rate for glass formation. For the 38Na2O–62SiO2, mol%, melt, analysis of Fig. 9 (and also Fig. 8(a)) predicts a critical cooling rate (R c) of 19±1°C/min. This is in excellent agreement with the value of 19°C/min determined for this composition by standard techniques [7], and this agreement strongly justifies the validity and usefulness of the newly developed method for measuring critical cooling rates for glass forming melts. The R c values for the VP2212 (Fig. 8(b)) and VP2076 (Fig. 8(c)) melts are 33±1°C/min and 41±2°C/min, respectively.
|
10.1016/j.jnoncrysol.2005.03.029
|
VP2076
| 0.683333
|
K/s
| -0.165367
|
A new DTA method for measuring critical cooling rate for glass formation. This is primarily the result of smaller, less sharp crystallization peaks (on cooling) for the VP2212 melt. The values of R c determined from the intercept of the straight lines in Fig. 13(a) and (b) on the lnR axis are ∼41 and ∼53°C/min for the VP2212 and VP2076 melts, respectively.
|
10.1016/j.jnoncrysol.2005.03.029
|
VP2212
| 0.683333
|
K/s
| -0.165367
|
A new DTA method for measuring critical cooling rate for glass formation. The nose temperature (T n) and nose time (t n) as estimated from Fig. 12(a) and (b) are 775°C and 5min for the VP2212 melt, and 818°C and 2min for the VP2076 melt. Based on these results, R c for the VP2212 melt is ∼30°C/min, and ∼42°C/min for the VP2076 melt.
|
10.1016/j.jnoncrysol.2005.03.029
|
VP2076
| 0.7
|
K/s
| -0.154902
|
Determination of forming ability of high pressure die casting for Zr-based metallic glass. For example, Hng et al. (1996) found the computed critical cooling rate of a Zr66Ni26Al8 BMG changes from 0.81K/s to 260K/s by using the fitted viscosity obtained by using above different assumptions. Therefore, it is essential to obtain the viscosity-temperature fitted data based on experimental measurements in order to obtain a more realistic estimation of the critical cooling rate to predict critical size of Zr55Y0.2 metallic glass by HPDC.
|
10.1016/j.jmatprotec.2017.01.015
|
Al8Ni26Zr66
| 0.81
|
K/s
| -0.091515
|
Bulk metallic glass composites containing B2 phase. By contrast, Co [4,73,133,153,155,163,164,287,288] and Hf [133,285] deteriorate the GFA. For example, for as-cast (Cu0.5Zr0.5)100-xAgx (x = 0, 2, 6, 10 at.%%) BMGs, with increasing Ag from 0 to 10 at.%%, the critical cooling rate ( R c ) decreases from 9.74 to 0.81 K/s [104].
|
10.1016/j.pmatsci.2021.100799
|
Ag10Cu45Zr45
| 0.81
|
K/s
| -0.091515
|
A new DTA method for measuring critical cooling rate for glass formation. This is primarily the result of smaller, less sharp crystallization peaks (on cooling) for the VP2212 melt. The values of R c determined from the intercept of the straight lines in Fig. 13(a) and (b) on the lnR axis are ∼41 and ∼53°C/min for the VP2212 and VP2076 melts, respectively.
|
10.1016/j.jnoncrysol.2005.03.029
|
VP2076
| 0.883333
|
K/s
| -0.053875
|
Prediction of the glass forming ability in Cu–Zr binary and Cu–Zr–Ti ternary alloys. Their corresponding critical cooling rates are listed in Table 6. It is seen that the critical cooling rates are reduced to 1.38×10^(2) K/s, 1.80×10^(2) K/s and 2.13×10^(2) K/s (Turnbull method), and 0.64K/s, 0.96K/s and 0.89K/s (TS method) for Cu60Zr32.5Ti7.5, Cu60Zr30Ti10 and Cu50Zr42.5Ti7.5 alloys, respectively.
|
10.1016/j.intermet.2007.07.008
|
Cu50Ti7.5Zr42.5
| 0.89
|
K/s
| -0.05061
|
Prediction of the glass forming ability in Cu–Zr binary and Cu–Zr–Ti ternary alloys. Their corresponding critical cooling rates are listed in Table 6. It is seen that the critical cooling rates are reduced to 1.38×10^(2) K/s, 1.80×10^(2) K/s and 2.13×10^(2) K/s (Turnbull method), and 0.64K/s, 0.96K/s and 0.89K/s (TS method) for Cu60Zr32.5Ti7.5, Cu60Zr30Ti10 and Cu50Zr42.5Ti7.5 alloys, respectively.
|
10.1016/j.intermet.2007.07.008
|
Cu60Ti10Zr30
| 0.96
|
K/s
| -0.017729
|
Metallic Glasses. While rapid quenching of the liquid by melt-spinning is the most common production method for metallic glasses, it is not necessary for all alloys. The multicomponent alloy Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 (at.%%), for example, has a critical cooling rate for glass formation of ∼1Ks^(-1), permitting casting to a fully glassy state in cross-sections of a few centimeters in conventional chill molds (Johnson 1999).
|
10.1016/B0-08-043152-6/00967-0
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
12 Functional bulk metallic glasses. The usual metallic glasses have poor GFA, and their critical cooling rate (R c) for the glass formation varies in the range of 104–107Ks^(-1). Whereas the R c of the BMGs ranges from 1 to 100Ks^(-1), for example, the R c of Vit1 is lower than 1Ks^(-1).
|
10.1016/B978-0-12-805056-9.00012-X
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Chapter 17 Chalcogenides for Phase-Change Memory. The temperature dependence of relative enthalpy, H, for PC processes is shown in Fig. 17.2 . The schematic form of H(T) is based on that for the bulk-metallic-glass-forming composition Zr52.5Cu17.9Ni14.6Al10.0Ti5.0 (at.%%) with a critical cooling rate of ~1Ks^(-1) [4], because similar data cannot be measured for the fast-crystallizing PC chalcogenides.
|
10.1016/B978-0-444-64062-8.00014-0
|
Al10Cu17.9Ni14.6Ti5Zr52.5
| 1
|
K/s
| 0
|
Thermodynamics, enthalpy relaxation and fragility of the bulk metallic glass-forming liquid Pd43Ni10Cu27P20. The Gibbs free energy difference between liquid and crystal, ΔG ^(l–x)(T), as a function of temperature is plotted in Fig. 11 together with values of other bulk metallic glass-forming liquids [2,12,36,38,41–43]. It is evident that the Pd43Ni10Cu27P20 alloy has a very low driving force for crystal nucleation, which is even lower than that of Zr41.2Ti13.8Cu12.5Ni10Be22.5 (Vit1), which has a critical cooling rate of 1 K/s.
|
10.1016/j.actamat.2003.10.003
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Enthalpy relaxation and its relation to the thermodynamics and crystallization of the Zr58.5Cu15.6Ni12.8Al10.3Nb2.8 bulk metallic glass-forming alloy. The entropy of fusion and the critical cooling rate of V106a are 8.03J/g-atom/K and 1.75K/s, respectively, which are comparable to the values of about 8.8J/g-atom/K and 1K/s for Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 (Vit1) [10]. These values are relatively small if compared with those of the ternary Mg64Cu25Y10 (about 11J/g-atom/K and 50K/s) [9], and those of the binary Zr62Ni38, which is known of having critical cooling rates of 10^(4) K/s [9,22].
|
10.1016/j.actamat.2006.09.040
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
The influence of shear rate and temperature on the viscosity and fragility of the Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 metallic-glass-forming liquid. Vit1 samples obtained from Liquidmetal Technologies are dehydrogenated at elevated temperature in a high vacuum environment and quenched to attain an amorphous state. In addition, dehydrogenated fully microcrystallized Vit1, with an estimated average microstructure length scale of 10^(-3) m [5], are prepared by cooling the melt slower than the critical cooling rate of 1Ks^(-1).
|
10.1016/j.actamat.2006.12.032
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Atomic structure of Zr41.2Ti13.8Cu12.5Ni10Be22.5 bulk metallic glass alloy. In this work, we present a detailed investigation of atomic structure of the vit1 BMG alloy by AIMD calculations. We chose the vit1 BMG alloy as the model system because it exhibits extraordinary GFA with a critical cooling rate as low as 1Ks^(-1) and up to 50mm in the critical dimension, large stability against crystallization in the supercooled liquid region and excellent mechanical properties [23–26].
|
10.1016/j.actamat.2008.09.022
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Elastic and viscoelastic properties of glassy, quasicrystalline and crystalline phases in Zr65Cu5Ni10Al7.5Pd12.5 alloys. Zr-based glassy alloys have a high glass-forming ability (GFA) compared to other transition metal (TM)-based alloys. Zr–LTM and Zr–LTM–NM (LTM=late transition metals; NM=noble metals) glassy alloys exhibit large critical diameters up to 30mm and critical cooling rates below 10Ks^(-1) [10,11], while Zr–LTM–Ti–Be alloys (e.g. Vit1) exhibit even lower critical cooling rates of about 1Ks^(-1) [12].
|
10.1016/j.actamat.2011.01.018
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Prediction of the glass forming ability in Cu–Zr binary and Cu–Zr–Ti ternary alloys. The values predicated by former equation seem larger, but those by latter is lower than the practical cooling rate. The deduction is easily obtained just by comparing these values with the critical cooling rate of Vit 1 alloy, of which the cooling rate is about 1K/s, and the critical thickness may reach as large as 50mm.
|
10.1016/j.intermet.2007.07.008
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Glass forming ability and a novel method for evaluating the thermoplastic formability of Zr x Ti65-x Be27.5Cu7.5 alloys. Coincidentally, this unusual phenomenon has been observed intensively. It is found that La55Al25Ni20 (R c = 67.5 K/s) and La55Al25Cu5Ni10Co5 (R c = 18.8 K/s) present lower values of ΔG than Vit1 (R c = 1 K/s) [76].
|
10.1016/j.intermet.2019.106600
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Synthesis and characterization of copper fiber reinforced Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 bulk metallic glass. Molten Vitreloy1 was infiltrated into the copper fibers using pressure-gravity method, with the help of Argon at a pressure of about 50kPa. Quenching was done within 60s in a water bucket to ensure the cooling rate higher than the required critical cooling rate of 1K/s for Vitreloy1.
|
10.1016/j.jallcom.2006.08.295
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Wf/Zr41.2Ti13.8Cu12.5Ni10Be22.5 bulk metallic glass composites prepared by a new melt infiltrating method. Bulk metallic glasses (BMGs) have many potential applications due to their unique properties, such as superior strength and hardness, excellent corrosion resistance and high wear resistance [1–5]. The Zr41.2Ti13.8Cu12.5Ni10Be22.5 (Vitreloy 1) BMG exhibits an exceptional glass forming ability with a critical cooling rate of ∼1K/s as well as shows a tensile strength of 1.9GPa and an elastic strain limit of 2% under compressive or tensile loading [6–8].
|
10.1016/j.jallcom.2010.02.045
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Thermodynamics and structural relaxation in Ce-based bulk metallic glass-forming liquids. The smaller the ΔG, the smaller the driving force of crystallization, and therefore the smaller nucleation and growth rate in the supercooled and the better glass-forming ability. This is consistent with the experimental results shown in Fig. 5, i.e. the smallest ΔG occurs for Pd43Ni10Cu27P20 alloy, which has the critical cooling rate of 1K/s (indicated in plot), while the largest ΔG is for Zr64Ni34 with a critical cooling rate of 10^(4) K/s.
|
10.1016/j.jallcom.2011.01.106
|
Cu27Ni10P20Pd43
| 1
|
K/s
| 0
|
Laser 3D printing of Zr-based bulk metallic glass. The results of many studies have suggested that the crystallization behavior of BMG between cooling from the liquid state into the amorphous and heating from the amorphous solid state was obviously asymmetric [27]. For example, the critical cooling rate R c of Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 BMG (Vit1) is approximately 1 K/s, however, the critical heating rate R h to prevent crystallization of Vit1 happening is two orders of magnitude larger than R c, which is about 200 K/s [28].
|
10.1016/j.jmapro.2019.02.020
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Laser additive manufacturing of laminated bulk metallic glass composite with desired strength-ductility combination. The crystalline behaviors of BMGs between cooling from the liquid state and heating from the amorphous solid state were obviously asymmetric, as can be observed in Fig. 6(a). For instance, the critical cooling rate R c of Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 BMG (Vit1) is approximately 1 K s^(–1), while the critical heating rate R h required to avoid crystallization of Vit1 is about 200 K s^(–1), two orders of magnitude larger than R c [59,60].
|
10.1016/j.jmst.2022.10.062
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Glass formation and crystallization behavior in Mg65Cu25Y10−x Gd x (x=0, 5 and 10) alloys. For Mg65Cu25Y10-x Gd x alloy system, T rg increases slightly from 0.54 to 0.55 with the increase of x from 0 to 5 and then again decreases to 0.54 with further increasing x to 10, i.e. the Mg65Cu25Gd10 and Mg65Cu25Y10 alloys have almost same value of T rg, although there is a much difference in GFA. The critical cooling rate for glass formation (R c) in the Mg65Cu25Gd10 alloy is estimated to be about ∼1 K/s [18], which is several orders of magnitude smaller than that of the Mg65Cu25Y10 alloy.
|
10.1016/j.jnoncrysol.2004.03.110
|
Cu25Gd10Mg65
| 1
|
K/s
| 0
|
Mechanical properties over the glass transition of Zr41.2Ti13.8Cu12.5Ni10Be22.5 bulk metallic glass. Conversely, at high temperatures (i.e. in the SLR), homogeneous flow can be obtained, resulting in a particularly large plastic stability. Among the recently developed BMG, the Zr41.2Ti13.8Cu12.5Ni10Be22.5 alloy (so-called Vit1) is one of the best glass former, with a critical cooling rate of approximately 1K/s [2].
|
10.1016/j.jnoncrysol.2005.06.012
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Crystallization prediction on laser three-dimensional printing of Zr-based bulk metallic glass. Many previous results have found that the crystallization behavior of BMG between cooling from the liquid state and heating from the amorphous solid state was obviously asymmetric [18,19]. For instance, the critical cooling rate R c of Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 BMG (Vit1) is approximately 1K/s, while the critical heating rate R h required to avoid crystallization of Vit1 is about 200K/s, two orders of magnitude larger than R c [20].
|
10.1016/j.jnoncrysol.2017.01.038
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Isothermal crystallization kinetics of an industrial-grade Zr-based bulk metallic glass. The low critical cooling rates R c , which are the minimum cooling rates required to vitrify BMG formers, on the order of 1 K/s of Zr-based BMGs, position them as one of the best BMG formers [5]. For example, the famous Vitreloy T M family BMGs Vit 1 (Zr 41.2 Ti 13.8 Cu 12.5 Ni 10.0 Be 22.5 in at.%%) and Vit 106a (Zr 58.5 Cu 15.6 Ni 12.8 Al 10.3 Nb 2.8 in at.%%) have critical cooling rates of 1 K/s and 1.75 K/s, respectively [6–8].
|
10.1016/j.jnoncrysol.2021.121145
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Shear yield and flow behavior of a zirconium-based bulk metallic glass. Liquidmetal-1 (LM-1, Zr41.25Ti13.75Ni10Cu12.5Be22.5) is a bulk metallic glass (BMG) that can be processed to fully amorphous conditions in large thicknesses (up to 10mm) because of its relatively low critical cooling rate (1K/s) (Peker and Johnson, 1993). Liquidmetal-1 (LM-1, Zr41.25Ti13.75Ni10Cu12.5Be22.5) is a bulk metallic glass (BMG) that can be processed to fully amorphous conditions in large thicknesses (up to 10mm) because of its relatively low critical cooling rate (1K/s) (Peker and Johnson, 1993).
|
10.1016/j.mechmat.2009.11.003
|
Be22.5Cu12.5Ni10Ti13.75Zr41.25
| 1
|
K/s
| 0
|
Dispersion technique studies on Pd43Ni10Cu27P20. Pd40Ni40P20 was discovered in 1984 as the first bulk metallic glass (BMG) forming alloy with a critical cooling rate as low as about 1K/s, when processed in B2O3 [1]. Pd40Ni40P20 was discovered in 1984 as the first bulk metallic glass (BMG) forming alloy with a critical cooling rate as low as about 1K/s, when processed in B2O3 [1].
|
10.1016/j.msea.2003.10.176
|
Ni40P20Pd40
| 1
|
K/s
| 0
|
Thermodynamic properties and metastability of bulk metallic glasses. In Fig. 7, ΔG(T) for several metallic glass forming alloys is shown including those processed in high precision microgravity experiments in recent space shuttle flights [59]: Curve: (1) Zr64Ni36 with a critical cooling rate R c>10^(5) K/s; (2) Ti34Zr11Cu47Ni8; (3) Zr65Al7.5Cu17.5Ni10; (4) Zr60Al10Cu18Ni9Co3; (5) Zr57Nb5Cu15.4Ni12.6Al10; and (6) Zr41.2Ti13.8Cu12.5Ni10Be22.5 with R c≈1K/s. Zr64Ni36 with a critical cooling rate R c>10^(5) K/s; Ti34Zr11Cu47Ni8; Zr65Al7.5Cu17.5Ni10; Zr60Al10Cu18Ni9Co3; Zr57Nb5Cu15.4Ni12.6Al10; and Zr41.2Ti13.8Cu12.5Ni10Be22.5 with R c≈1K/s.
|
10.1016/j.msea.2003.10.254
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Wear resistance of Zr-based bulk metallic glass applied in bearing rollers. Since the successful preparation of Zr41.2Ti13.8Cu12.5Ni10.0Be22.5 bulk metallic glass (BMG) by Peker and Johnson in 1993, Zr-based BMG has attracted much attention [1,2]. Because this material has a very low critical cooling rate, ∼1K/s, for formation of BMG, it is possible to produce it into rods or plates to several tens of millimetre.
|
10.1016/j.msea.2004.07.054
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Deformation and crystallization of a Zr41.2Ti13.8Cu12.5Ni10Be22.5 bulk metallic glass in the supercooled liquid region. Thus, BMGs are considered as promising structural materials, e.g. in the field of near net shape fabrication of structural components. Among the multi-component BMGs, the zirconium-based alloy Zr41.2Ti13.8Cu12.5Ni10Be22.5 (Vitreloy 1) is a particularly good glass former with a critical cooling rate as low as approximately 1K/s [4].
|
10.1016/j.msea.2006.07.050
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
A study of the glass forming ability in ZrNiAl alloys. Their strength can be as high as 2GPa, and elastic strain is approximately 2%, which are substantially higher than those of the most crystalline alloys. One of the most highly processible BMGs is alloy Zr41Ti14Cu12.5Ni10Be22.5, which has a critical cooling rate of about 1K/s [5].
|
10.1016/j.msea.2006.08.109
|
Be22.5Cu12.5Ni10Ti14Zr41
| 1
|
K/s
| 0
|
Micro-forming and surface evaluation of Zr41Ti14Cu12.5Ni10Be22.5 bulk metallic glass. Also, using normalized roughness, a new parameter is suggested as a measure of micro-formability of different forming conditions. The reason to use vit 1 is that it is one of the best BMG's showing excellent glass forming ability with critical cooling rate of 1K/s [12] and low viscosity sufficient to micro-forming.
|
10.1016/j.msea.2006.10.153
|
Be22.5Cu12.5Ni10Ti14Zr41
| 1
|
K/s
| 0
|
The influence of cooling rate on the hardness of Pd–Si binary glassy alloys. According to the effects of structural relaxation on the property changes of conventional metallic glasses induced by annealing, different cooling rates would result in the variation in glass transition temperature, density, structure sensitive properties such as hardness, and other properties. Recently, some bulk metallic glasses exhibited a very low R c, such as 1.0K/s for the Pd40Ni10Cu30P20 BMG [15].
|
10.1016/j.msea.2007.03.094
|
Cu30Ni10P20Pd40
| 1
|
K/s
| 0
|
Bulk metallic glasses. Vitalloy 1 (vit1), one of the most extensively studied BMG in the family, has the composition of Zr41Ti14Cu12.5Ni10Be22.5. Its temperature–time transition (TTT) diagram has the “nose” of the nucleation curve for crystals at time scales of the order 10^(2) s and the critical cooling rates for glass formation in the 1K/s range.
|
10.1016/j.mser.2004.03.001
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
3D printing of bulk metallic glasses. A representative example of the alloy Zr55Cu30Ni5Al10 with a critical cast diameter of 30 mm has been successfully developed [8]. Peker and Johnson have also developed another important glass former (Zr41.2Ti13.8Cu12.5Ni10.0Be22.5) with a critical cooling rate down of only 1 K/s, which became the first commercial BMG (originally named Vit 1) [9].
|
10.1016/j.mser.2021.100625
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
On the crystalline equilibrium phases of the Zr57Cu15.4Ni12.6Al10Nb5 bulk metallic glass forming alloy. Vit 106 has a critical cooling rate of 10 Ks^(-1) [9]. It has moderate glass forming ability when compared to Zr41.2Ti13.8Cu12.5Ni10Be22.5, which has a critical cooling rate of 1 Ks^(-1) [10].
|
10.1016/j.scriptamat.2003.12.023
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Influence of structural relaxation on the fatigue behavior of a Zr41.25Ti13.75Ni10Cu12.5Be22.5 bulk amorphous alloy. The kinetic glass transition involves sudden changes of the specific heat capacity [26] and the expansion coefficient [27], while free volume, enthalpy, and configurational entropy are frozen in. Noting that the Zr–Ti–Ni–Cu–Be glass-forming system has a very low critical cooling rate of about 1K/s [3,28], differences in the cooling rate above this critical value may result in variations in the physical and thermodynamic properties, in particular the enthalpy and free volume of the system.
|
10.1016/j.scriptamat.2005.09.048
|
Be22.5Cu12.5Ni10Ti13.75Zr41.25
| 1
|
K/s
| 0
|
Microhardness and abrasive wear resistance of metallic glasses and nanostructured composite materials. Before 1990, Fe-, Co- and Ni-based amorphous alloys were formed by using high cooling rates but the resulting sample thickness was limited to less than about 50 μm [2] reducing their potential as engineering materials. However, in 1984, an exceptional example, Pd40Ni40P20 was discovered as the first bulk metallic glass (BMG) forming alloy with a critical cooling rate as low as about 1 Ks^(-1) when processed in B2O3 [3].
|
10.1016/S0022-3093(02)01941-5
|
Ni40P20Pd40
| 1
|
K/s
| 0
|
Microhardness and abrasive wear resistance of metallic glasses and nanostructured composite materials. On the other hand, in order to develop some of the best bulk glass-forming alloys, Johnson [16] has successfully added suitable components (Cu, Ni) to lower the eutectic temperature in the Zr–Ti–Be system obtaining the family of Zr–Ti–Cu–Ni–Be glasses. These alloys show an exceptional glass forming ability and a critical cooling rate as low as about 1 Ks^(-1) such as for Vitreloy^(™), which makes them very interesting materials for engineering applications [7].
|
10.1016/S0022-3093(02)01941-5
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Thermodynamics and kinetics of the Zr41.2Ti13.8Cu10.0Ni12.5Be22.5 bulk metallic glass forming liquid: glass formation from a strong liquid. In the following we will present results from viscosity measurements on the Zr 41.2 Ti 13.8 Cu 10.0 Ni 12.5 Be 22.5 (Vit1) BMG forming alloy [8]. With a critical cooling rate for crystallization of 1 Ks^(-1) it is one of the best metallic glass forming systems [9] and thermodynamic data [10] and specific volume measurements [11] are already available.
|
10.1016/S0022-3093(99)00133-7
|
Be22.5Cu10Ni12.5Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Nanocrystallization of Zr–Ti–Cu–Ni–Be bulk metallic glass. The critical cooling rate for the glass forming is ranged from several to several hundred K/s so that amorphous samples with the thickness in the order of mm or even cm can be fabricated [2,3], which implies that the fully amorphous alloys can be prepared using conventional cast techniques. Among them, Zr41.2Ti13.8Cu12.5Ni10Be22.5 bulk metallic glass attracts special attention in the last few years, not only because of its high glass forming ability (R c=1 K/s) [4], excellent mechanical and engineering properties, but also as one of the representative examples of fundamental condensed-matter studies [5–9].
|
10.1016/S0167-577X(02)01222-3
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Crystallization behavior of the bulk metallic glass forming Zr41Ti14Cu12Ni10Be23 liquid. This diagram reveals a large asymmetry in the crystallization behavior between cooling from the stable melt and heating the amorphous sample. In agreement with previous results [12], we found a critical cooling rate for Vit 1 of about 1K/s.
|
10.1016/S0921-5093(00)01454-4
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Thermodynamics and kinetics of Zr–Ti–Cu–Ni–Be bulk metallic glass forming liquids. In Fig. 6 , the Gibbs free enthalpy difference between the supercooled liquid and the crystalline mixture is compared with a selection of other eutectic, or close to eutectic, glass forming systems. The alloys show different critical cooling rates between 1K/s for the pentary Vit 1 and about 10^(4) K/s for the binary Zr62Ni38.
|
10.1016/S0921-5093(00)01458-1
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Preparation and super-plastic deformation of the Zr-based bulk metallic glass. In addition, bulk metallic glasses have been found to have excellent mechanical properties, high wear resistance and high corrosion resistance [5], which offer great potential for commercial applications. One of the most highly processible bulk metallic glass is Zr41Ti14Cu12.5Ni10Be22.5, which has a critical cooling rate of about 1 K s^(-1) [6].
|
10.1016/S0921-5093(03)00370-8
|
Be22.5Cu12.5Ni10Ti14Zr41
| 1
|
K/s
| 0
|
Thermodynamics of La based La–Al–Cu–Ni–Co alloys studied by temperature modulated DSC. Therefore, the small Gibbs free energy difference for bulk glass formers could be one crucial point in understanding the high glass forming ability. However, the Gibbs free energy differences for the present La base alloys, which have critical cooling rates between 18.8 and 67.7 K/s, are even smaller than that of Zr41.2Ti13.8Cu12.5Ni10Be22.5 alloy which has a critical cooling rate of 1 K/s.
|
10.1016/S0966-9795(99)00159-4
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Mechanical properties of Zr56.2Ti13.8Nb5.0Cu6.9Ni5.6Be12.5 ductile phase reinforced bulk metallic glass composite. The Zr41.2Ti13.8Cu12.5Ni10Be22.5 (Vitreloy 1) bulk metallic glass exhibits an exceptional glass forming ability with a critical cooling rate of ∼1K/s, which makes it a very interesting material for structural applications. The Zr41.2Ti13.8Cu12.5Ni10Be22.5 (Vitreloy 1) bulk metallic glass exhibits an exceptional glass forming ability with a critical cooling rate of ∼1K/s, which makes it a very interesting material for structural applications.
|
10.1016/S1359-6454(01)00068-4
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Transition from nucleation controlled to growth controlled crystallization in Pd43Ni10Cu27P20 melts. In 1984 Pd40Ni40P20 has been discovered as the first bulk metallic glass (BMG) forming alloy with a critical cooling rate as low as about 1 K/s when processed in B2O3 [1]. In 1984 Pd40Ni40P20 has been discovered as the first bulk metallic glass (BMG) forming alloy with a critical cooling rate as low as about 1 K/s when processed in B2O3 [1].
|
10.1016/S1359-6454(01)00159-8
|
Ni40P20Pd40
| 1
|
K/s
| 0
|
The effects of hydrogen on viscoelastic relaxation in Zr–Ti–Ni–Cu–Be bulk metallic glasses: implications for hydrogen embrittlement. Moreover, some Zr and Ti based metallic glasses have been considered as hydrogen-storage materials where potential embrittling effects of internal hydrogen are of significant concern [8]. Among the bulk metallic glasses, a Zr–Ti–Ni–Cu–Be alloy (Vitreloy 1) is one of the best glass formers, with a critical cooling rate as low as 1 K/s [9].
|
10.1016/S1359-6454(01)00359-7
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Formation and properties of Zr48Nb8Cu14Ni12Be18 bulk metallic glass. The Zr-based BMGs exhibit unique mechanical properties as well as good wear and corrosion resistance, which could be used in fine optical machinery parts, writing tools, sporting goods and electrodes for generation of chloride gas. Zr65Al7.5Ni10Cu17.5 [2], Zr57.5Al7.5Ni10Cu20Ti5 [4], Zr41Ti14Cu12.5Ni10Be22.5 [1] and Zr57Al10Ni12.6Cu15.4Nb5 [5] are typical Zr-based BMGs exhibiting excellent glass forming ability (GFA) and high thermal stability, the alloy Zr41Ti14Cu12.5Ni10Be22.5 is the best glass former with a critical cooling rate of approximately 1 K/s [3].
|
10.1016/S1359-6454(02)00602-X
|
Be22.5Cu12.5Ni10Ti14Zr41
| 1
|
K/s
| 0
|
Equilibrium viscosity of the Zr41.2Ti13.8Cu12.5Ni10Be22.5 bulk metallic glass-forming liquid and viscous flow during relaxation, phase separation, and primary crystallization. As a result, both parallel plate rheometry and three-point beam bending, previously used in the study of silicate glasses and polymers, can now be utilized to measure the viscosity of BMG alloys well into the supercooled liquid region[6, 7]. Of these recent multicomponent BMG alloys, Zr41.2Ti13.8Cu12.5Ni10Be22.5 is the best glass former, with a critical cooling rate of approximately 1K/s[8].
|
10.1016/S1359-6454(98)00242-0
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1
|
K/s
| 0
|
Spark welding of Zr55Al10Ni5Cu30 bulk metallic glasses. It has been reported that TTT diagram of the crystallization on heating of glassy solid was different from that on cooling of melt. In a Zr41Ti14Cu12Ni10Be23 alloy, the critical cooling rate of the melt for circumvent crystallization is about 1 K/s, and the critical heating rate from the amorphous state to the melt for prevention of the crystallization is about 200 K/s [15–17].
|
10.1016/S1359-6462(01)01003-X
|
Be23Cu12Ni10Ti14Zr41
| 1
|
K/s
| 0
|
Materials properties measurements and particle beam interactions studies using electrostatic levitation. The measured critical cooling rates leading to glass formation, for the processed LS and Pt-LS glasses, were 14±2°C/min and 130±5°C/min, respectively. The same compositions processed with a crucible yielded to critical cooling rates of 62±3°C/min and 162±5°C/min, respectively.
|
10.1016/j.mser.2013.12.001
|
Li2O6Si2
| 1.033333
|
K/s
| 0.01424
|
Utilization of high entropy alloy characteristics in Er-Gd-Y-Al-Co high entropy bulk metallic glass. With increasing annealing temperature (T/T x = 0.955) in Vit105, the average diameters of the crystalline phases increase up to 15 nm for 200 min annealing, which means that annealing temperature is a crucial factor to decide the resistance to crystal growth. In particular, the diameters of the crystalline phases in Zr41·2Ti13·8Cu12·5Ni10Be22.5 (Vit1, R c = 1.4 K/s) [55] are all 10.5 nm with single-modal distribution of the crystalline size at T/T x = 0.926 for 100 min annealing, but the crystalline sizes are 10.33 ± 1.55 nm, 19.51 ± 5.85 nm and 58.43 ± 7.78 nm at T/T x = 0.967 for 8 min annealing, suggesting the multi-modal distribution.
|
10.1016/j.actamat.2018.06.024
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1.4
|
K/s
| 0.146128
|
First principles modeling of the structural, electronic, and vibrational properties of Ni40Pd40P20 bulk metallic glass. Currently, a wide range of multi-component BMG alloys [5,11] exists; however, the industrial production of BMGs remains a difficult problem due to the requirement of high cooling rates to produce a metallic glass with a thickness on the macroscopic length scale. Ni40Pd40P20 was first prepared by Turnbull and co-workers, [12,13] who employed a critical cooling rate of about 1.4 K/s and the application of B2O3 fluxing method to purify the melt and avoid heterogeneous nucleation.
|
10.1016/j.nocx.2018.100004
|
Ni40P20Pd40
| 1.4
|
K/s
| 0.146128
|
Laser solid forming Zr-based bulk metallic glass. Fig. 7(b) shows that the average heating and cooling rates from Tg to Tm at point α shown in Fig. 7(a), which is at the center of the top center of the molten pool, were 4.3 × 10^(6) °C s^(-1) and 3.7 × 10^(4) °C s^(-1) respectively. While the critical cooling rate for the amorphous formation of Zr65Al7.5Ni10Cu17.5 is 1.5 °C s^(-1) [12].
|
10.1016/j.intermet.2011.10.008
|
Al7.5Cu17.5Ni10Zr65
| 1.5
|
K/s
| 0.176091
|
Electronic structure of Pd42.5Ni7.5Cu30P20, an excellent bulk metallic glass former: Comparison to the Pd40Ni40P20 reference glass. Although several thermodynamic and mechanical properties have been investigated in detail in Pd–Ni–Cu–P glassy alloys [2], only a few basic attempts have been made, from the viewpoints of their structural and electronic properties, to understand why they have such excellent GFA. Electrical conductivity (σ) measurements for the Pd42.5Ni7.5Cu30P20 metallic glass [5] showed that σ decreases by mainly exchanging Ni with Cu atoms from the Pd40Ni40P20 reference glass [6], which has a worse critical cooling rate of 1.6K/s [7], suggesting a decrease of electronic density of states (DOS) at the Fermi energy, N(E F).
|
10.1016/j.actamat.2007.01.041
|
Ni40P20Pd40
| 1.6
|
K/s
| 0.20412
|
Soft X-ray emission study of Pd–Ni–Cu–P bulk metallic glass. From this result, a selective formation of the Pd–P covalent bonds is suggested. Conduction-band DOS were also measured using in-house PES and inverse-photoemission spectroscopy (IPES) [4] on the Pd42.5Ni7.5Cu30P20 glass and the reference glass Pd40Ni40P20, which has a slightly worse critical-cooling-rate of 1.6K/s [5].
|
10.1016/j.elspec.2006.12.061
|
Ni40P20Pd40
| 1.6
|
K/s
| 0.20412
|
Formation of amorphous Zr41.2Ti13.8Ni10Cu12.5Be22.5 coatings via the ElectroSpark Deposition process. Fig. 7 presents a continuous cooling curve for the crystallization of Vitreloy^(®) 1 from a liquid state (bold curve). As can be observed, the critical cooling rate required to form a completely amorphous structure during solidification was 1.7K/s.
|
10.1016/j.intermet.2007.12.013
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1.7
|
K/s
| 0.230449
|
Kinetics of crystallization in continuously cooled BMG. Continuous cooling transformation (CCT) diagram of Zr41.2Ti13.8Cu12.5Ni10Be22.5 alloy has been calculated. The calculated critical cooling rates R c of the alloy is 1.7K/s, which is in good agreement with the experimental value.
|
10.1016/j.msea.2005.05.038
|
Be22.5Cu12.5Ni10Ti13.8Zr41.2
| 1.7
|
K/s
| 0.230449
|
Enthalpy relaxation and its relation to the thermodynamics and crystallization of the Zr58.5Cu15.6Ni12.8Al10.3Nb2.8 bulk metallic glass-forming alloy. It can be vitrified via conventional processing techniques such as arc melting without subsequent mold casting. It has a large supercooled liquid region and can be prepared with critical cooling rates as low as 1.75K/s, which correspond to a critical casting thicknesses of greater than 1.5cm.
|
10.1016/j.actamat.2006.09.040
|
Al10.3Cu15.6Nb2.8Ni12.8Zr58.5
| 1.75
|
K/s
| 0.243038
|
End of preview. Expand
in Data Studio
Extracting Accurate Materials Data from Research Papers with Conversational Language Models and Prompt Engineering
Dataset containing LLM-derived experimental critical cooling rates of 297 metallic glasses
Dataset Information
- Source: Foundry-ML
- DOI: 10.18126/ndyp-yv32
- Year: 2024
- Authors: Polak, Maciej P., Morgan, Dane
- Data Type: tabular
Fields
| Field | Role | Description | Units |
|---|---|---|---|
| Passage | input | Text passage LLM found to get data | |
| DOI | input | Original data reference | |
| Material | input | Material composition | |
| Rc | input | Critical cooling rate | K/s |
| Unit | input | Critical cooling rate units | |
| log(Rc) | target | Critical cooling rate (log scale) | K/s |
Splits
- train: train
Usage
With Foundry-ML (recommended for materials science workflows)
from foundry import Foundry
f = Foundry()
dataset = f.get_dataset("10.18126/ndyp-yv32")
X, y = dataset.get_as_dict()['train']
With HuggingFace Datasets
from datasets import load_dataset
dataset = load_dataset("Dataset_metallicglass_Rc_LLM")
Citation
@misc{https://doi.org/10.18126/ndyp-yv32
doi = {10.18126/ndyp-yv32}
url = {https://doi.org/10.18126/ndyp-yv32}
author = {Polak, Maciej P. and Morgan, Dane}
title = {Extracting Accurate Materials Data from Research Papers with Conversational Language Models and Prompt Engineering}
keywords = {machine learning, foundry}
publisher = {Materials Data Facility}
year = {root=2024}}
License
other
This dataset was exported from Foundry-ML, a platform for materials science datasets.
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