Bulk nickel-phosphorus-silicon glasses bearing manganese

Abstract

The disclosure is directed to NiPSi alloys bearing Mn and optionally Cr, Mo, Nb, and Ta that are capable of forming a metallic glass, and more particularly demonstrate critical rod diameters for glass formation greater than 1 mm and as large as 5 mm or larger.

Claims

1. An alloy capable of forming a metallic glass represented by the following formula (subscripts denote atomic percentages):
Ni.sub.(100-a-b-c-d)Mn.sub.aX.sub.bP.sub.cSi.sub.d where: a is between 0.25 and 12, b is up to 20, c is between 14 and 22, d is between 0.25 and 5, and where X is selected from Cr, Mo, Nb, Ta, and combinations thereof or by the above formula and wherein: i) up to 50 atomic percent of Ni is substituted by Co, ii) up to 30 atomic percent of Ni is substituted by Fe, iii) up to 10 atomic percent of Ni is substituted by Cu, or iv) up to 2 atomic percent of Ni is substituted by Ge, V, Sn, W, Ru, Re, Pd, Pt, or a combination thereof.

2. The alloy according to claim 1, wherein X is selected from Cr and Mo, and combinations thereof, and b is up to 18 percent.

3. The alloy according to claim 1, wherein X is selected from Nb and Ta, and combinations thereof, and b is up to 6 percent.

4. The alloy according to claim 1, wherein X is Mo and Nb.

5. The alloy according to claim 4, wherein the atomic concentration of Mo is between 0.5 and 4 atomic percent, and the critical rod diameter of the alloy is at least 1 mm.

6. The alloy according to claim 4, wherein the atomic concentration of Nb is between 2.5 and 5 atomic percent, and the critical rod diameter of the alloy is at least 2 mm.

7. The alloy according to claim 1, wherein X is Cr.

8. The alloy according to claim 7, wherein a is between 1 and 7, and the critical rod diameter of the alloy is at least 1 mm.

9. The alloy according to claim 7, wherein b is between 5 and 15, and the critical rod diameter of the alloy is at least 1 mm.

10. The alloy according to claim 7, wherein c is between 15 and 21, and the critical rod diameter of the alloy is at least 1 mm.

11. The alloy according to claim 7, wherein d is between 0.25 and 3, and the critical rod diameter of the alloy is at least 1 mm.

12. The alloy according to claim 1, wherein up to 50 atomic percent of Ni is substituted with Co.

13. The alloy according to claim 1, wherein up to 30 atomic percent of Ni is substituted by Fe.

14. The alloy according to claim 1, wherein up to 10 atomic percent of Ni is substituted by Cu.

15. The alloy according to claim 1, wherein the alloy further comprises Ge, V, Sn, W, Ru, Re, Pd, Pt, or a combination thereof at combined atomic concentration of up to 2 percent.

16. A metallic glass comprising an alloy, wherein a composition of the alloy is represented by the following formula (subscripts denote atomic percentages):
Ni.sub.(100-a-b-c-d)Mn.sub.aX.sub.bP.sub.cSi.sub.d where: a is between 0.25 and 12, b is up to 20, c is between 14 and 22, d is between 0.25 and 5, and where X is selected from Cr, Mo, Nb, Ta, and combinations thereof.

17. A method of producing a metallic glass comprising: melting an alloy into a molten state to form an alloy melt; where the alloy has a composition represented by the following formula (subscripts denote atomic percentages):
Ni.sub.(100-a-b-c-d)Mn.sub.aX.sub.bP.sub.cSi.sub.d where: a is between 0.25 and 12, b is up to 20, c is between 14 and 22, d is between 0.25 and 5, where X is selected from Cr, Mo, Nb, Ta, and combinations thereof; and quenching the alloy melt at a cooling rate sufficiently rapid to prevent crystallization of the alloy.

18. The method of claim 17, further comprising fluxing the alloy melt with a reducing agent prior to quenching.

19. The method of claim 17, wherein the temperature of the alloy melt prior to quenching is at least 1100 C.

20. The method of claim 17, wherein the temperature of the alloy melt prior to quenching is at least 100 C. above the liquidus temperature of the alloy.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) The description will be more fully understood with reference to the following figures and data graphs, which are presented as various embodiments of the disclosure and should not be construed as a complete recitation of the scope of the disclosure.

(2) FIG. 1 provides a plot showing the effect of substituting Ni with Mn on the glass-forming ability of Ni.sub.80.5-xMn.sub.xP.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure.

(3) FIG. 2 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.80.5-xMn.sub.xP.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition, crystallization, solidus, and liquidus temperatures, respectively.

(4) FIG. 3 provides a plot showing the effect of substituting P with Si on the glass-forming ability of Ni.sub.74Mn.sub.6.5P.sub.19.5-xSi.sub.x alloys in accordance with embodiments of the disclosure.

(5) FIG. 4 provides a plot showing calorimetry scans for sample amorphous alloys Ni.sub.74Mn.sub.6.5P.sub.19.5-xSi.sub.x in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition, crystallization, solidus, and liquidus temperatures, respectively.

(6) FIG. 5 provides a plot showing the effect of varying the metal to metalloid ratio, according to the formula (Ni.sub.0.919Mn.sub.0.081).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x in accordance with embodiments of the disclosure.

(7) FIG. 6 provides a plot showing calorimetry scans for sample amorphous alloys (Ni.sub.0.919Mn.sub.0.081).sub.100-x(P.sub.0.923B.sub.0.077).sub.x in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition, crystallization, solidus, and liquidus temperatures, respectively.

(8) FIG. 7 provides an optical image of a 3 mm metallic glass rod of example alloy Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 in accordance with an embodiment of the disclosure.

(9) FIG. 8 provides an x-ray diffractogram verifying the amorphous structure of a 3 mm metallic glass rod of example alloy Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 in accordance with an embodiment of the disclosure.

(10) FIG. 9 provides an optical image of a plastically bent 1 mm metallic glass rod of example alloy Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 in accordance with an embodiment of the t disclosure.

(11) FIG. 10 provides a plot showing the effect of substituting Mo with Mn on the glass-forming ability of Ni.sub.72.5-xMo.sub.4-xNb.sub.4Mn.sub.xP.sub.18Si.sub.1.5 alloys in accordance with embodiments of the disclosure.

(12) FIG. 11 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.72.5-xMo.sub.4-xNb.sub.4Mn.sub.xP.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition, crystallization, solidus, and liquidus temperatures, respectively.

(13) FIG. 12 provides a plot showing the effect of substituting Ni with Mn on the glass-forming ability of Ni.sub.74.5-xMo.sub.2.5Nb.sub.3.5Mn.sub.xP.sub.18Si.sub.1.5 alloys in accordance with embodiments of the disclosure.

(14) FIG. 13 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.74.5-xMo.sub.2.5Nb.sub.3.5Mn.sub.xP.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition, crystallization, solidus, and liquidus temperatures, respectively.

(15) FIG. 14 provides a plot showing the effect of substituting Nb with Mo on the glass-forming ability of Ni.sub.72.5-xMo.sub.xNb.sub.6-xMn.sub.2P.sub.18Si.sub.1.5 alloys in accordance with embodiments of the disclosure.

(16) FIG. 15 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.72.5-xMo.sub.xNb.sub.6-xMn.sub.2P.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition, crystallization, solidus, and liquidus temperatures, respectively.

(17) FIG. 16 provides an optical image of a 3 mm metallic glass rod of example alloy Ni.sub.73Mo.sub.2.5Nb.sub.3.5Mn.sub.1.5P.sub.18Si.sub.1.5 in accordance with an embodiment of the disclosure.

(18) FIG. 17 provides an x-ray diffractogram verifying the amorphous structure of a 3 mm metallic glass rod of example alloy Ni.sub.73Mo.sub.2.5Nb.sub.3.5Mn.sub.1.5P.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure.

(19) FIG. 18 provides a plot showing the effect of substituting Ni with Cr on the glass-forming ability of Ni.sub.77.5-xCr.sub.xMn.sub.3P.sub.18Si.sub.1.5 alloys in accordance with embodiments of the disclosure.

(20) FIG. 19 provides a plot showing the effect of substituting Ni with Mn on the glass-forming ability of Ni.sub.71-xCr.sub.9.5Mn.sub.xP.sub.18Si.sub.1.5 alloys in accordance with embodiments of the disclosure.

(21) FIG. 20 provides a plot showing the effect of substituting P with Si on the glass-forming ability of Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19.5-xSi.sub.x alloys in accordance with embodiments of the disclosure.

(22) FIG. 21 provides a plot showing the effect of varying the ratio of metals to metalloids on the glass-forming ability of (Ni.sub.0.839Cr.sub.0.118Mn.sub.0.043).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x alloys in accordance with embodiments of the disclosure.

(23) FIG. 22 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.77.5-xCr.sub.xMn.sub.3P.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, solidus temperature T.sub.s, and liquidus temperature T.sub.l.

(24) FIG. 23 provides a plot showing the effect of substituting Ni with Cr on the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and the difference between the glass-transition temperature and the crystallization temperature, T=T.sub.xT.sub.g, for Ni.sub.77.5-xCr.sub.xMn.sub.3P.sub.18Si.sub.1 metallic glasses in accordance with embodiments of the disclosure.

(25) FIG. 24 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.71-xCr.sub.9.5Mn.sub.xP.sub.18Si.sub.1.5 in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, solidus temperature T.sub.s, and liquidus temperature T.sub.l.

(26) FIG. 25 provides a plot showing the effect of substituting Ni with Mn on the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and the difference between the glass-transition temperature and the crystallization temperature, T=T.sub.xT.sub.g, for Ni.sub.71-xCr.sub.9.5Mn.sub.xP.sub.18Si.sub.1.5 metallic glasses in accordance with embodiments of the disclosure.

(27) FIG. 26 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19.5-xSi.sub.x in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, solidus temperature T.sub.s, and liquidus temperature T.sub.l.

(28) FIG. 27 provides a plot showing the effect of substituting P with Si on the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and the difference between the glass-transition temperature and the crystallization temperature, T=T.sub.xT.sub.g, for Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19.5-xSi.sub.x metallic glasses in accordance with embodiments of the disclosure.

(29) FIG. 28 provides a plot showing calorimetry scans for sample metallic glasses Ni.sub.0.839Cr.sub.0.118Mn.sub.0.043).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x in accordance with embodiments of the disclosure. Arrows from left to right designate the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, solidus temperature T.sub.s, and liquidus temperature T.sub.l.

(30) FIG. 29 provides a plot showing the effect of varying the total concentration of metals and metalloids on the glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and the difference between the glass-transition temperature and the crystallization temperature, T=T.sub.xT.sub.g, for Ni.sub.0.839Cr.sub.0.118Mn.sub.0.043).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x metallic glasses in accordance with embodiments of the disclosure.

(31) FIG. 30 provides an image of an amorphous 5 mm rod of example metallic glass Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 in accordance with embodiments of the disclosure.

(32) FIG. 31 provides an x-ray diffractogram verifying the amorphous structure of a 5 mm rod of example metallic glass Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 in accordance with embodiments of the disclosure.

(33) FIG. 32 provides a compressive stress-strain diagram for example metallic glass Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 in accordance with embodiments of the disclosure.

(34) FIG. 33 provides an image of a plastically bent 1 mm amorphous rod of example metallic glass Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 in accordance with embodiments of the disclosure.

DETAILED DESCRIPTION

(35) The disclosure is directed to alloys, metallic glasses, and methods of making and using the same. In some aspects, the alloys are described as capable of forming metallic glasses having certain characteristics. It is intended, and will be understood by those skilled in the art, that the disclosure is also directed to metallic glasses formed of the disclosed alloys described herein.

(36) In the disclosure it was discovered that B-free NiMnPSi alloys that may also contain Cr, Mo, Nb, and Ta are capable of forming metallic glasses.

Definitions

(37) In the disclosure, B-free alloy refers to an alloy that contains B up to atomic fractions that are consistent with incidental impurity. In some embodiments, alloys in accordance with the disclosure contain B in atomic concentrations of less than 0.1 percent. In other embodiments, alloys in accordance with the disclosure contain B in atomic concentrations of less than 0.05 percent. In yet other embodiments, alloys in accordance with the disclosure contain B in atomic concentrations of less than 0.01 percent.

(38) In the disclosure, the glass-forming ability of each alloy is quantified by the critical rod diameter, defined as the largest rod diameter in which the amorphous phase (i.e. the metallic glass) can be formed when processed by a method of water quenching a quartz tube having 0.5 mm thick walls containing a molten alloy.

(39) A critical cooling rate, which is defined as the cooling rate required to avoid crystallization and form the amorphous phase of the alloy (i.e. the metallic glass), determines the critical rod diameter. The lower the critical cooling rate of an alloy, the larger its critical rod diameter. The critical cooling rate R.sub.c in K/s and critical rod diameter d.sub.c in mm are related via the following approximate empirical formula:
R.sub.c=1000/d.sub.c.sup.2Eq. (2)
According to Eq. (2), the critical cooling rate for an alloy having a critical rod diameter of about 3 mm, as in the case of the alloys according to embodiments of the disclosure, is only about 10.sup.2 K/s.

(40) Generally, three categories are known in the art for identifying the ability of a metal alloy to form glass (i.e. to bypass the stable crystal phase and form an amorphous phase). Metal alloys having critical cooling rates in excess of 10.sup.12 K/s are typically referred to as non-glass formers, as it is physically impossible to achieve such cooling rates over a meaningful thickness (i.e. at least 1 micrometer). Metal alloys having critical cooling rates in the range of 10.sup.5 to 10.sup.12 K/s are typically referred to as marginal glass formers, as they are able to form glass over thicknesses ranging from 1 to 100 micrometers according to Eq. (2). Metal alloys having critical cooling rates on the order of 10.sup.3 or less, and as low as 1 or 0.1 K/s, are typically referred to as bulk glass formers, as they are able to form glass over thicknesses ranging from 1 millimeter to several centimeters. The glass-forming ability of a metallic alloy is, to a large extent, dependent on the composition of the alloy. The compositional ranges for alloys capable of forming marginal glass formers are considerably broader than those for forming bulk glass formers.

(41) In the disclosure, the stability of the supercooled liquid against crystallization is defined as the difference between the crystallization temperature T.sub.x and the glass-transition temperature T.sub.g, T=T.sub.xT.sub.g, as measured by scanning calorimetry at heating rate of 20 C./min.

Example Alloy System 1: NiMnPSi

(42) In one embodiment of the disclosure, Ni-based alloys with a Mn content of between 0.5 and 10 atomic percent, a P content of between 16 and 21 atomic percent, and a Si content of between 0.5 and 3 atomic percent are capable of forming a metallic glass. In another embodiment, alloys with a Mn content of about 6 to 7 atomic percent, P content of about 17.5 to 18.5 atomic percent, and Si content of about 1 to 2 atomic percent, demonstrate a critical rod diameter of at least 3 mm.

(43) Sample metallic glasses (Samples 1-6), in accordance with embodiments of the disclosure, showing the effect of substituting Ni with Mn, according to the formula Ni.sub.80.5-xMn.sub.xP.sub.18Si.sub.1.5, are presented in Table 1 and FIG. 1. As shown, when the Mn atomic concentration x is between 3 and 8.5 percent, the critical rod diameter is at least 1 mm. More specifically, when the Mn atomic concentration x is at between 6 and 7 percent, the critical rod diameter is 2 to 3 mm. Differential calorimetry scans for the sample metallic glasses in which Ni is substituted with Mn are presented in FIG. 2.

(44) TABLE-US-00001 TABLE 1 Sample alloys demonstrating the effect of increasing the Mn atomic concentration at the expense of Ni on the glass-forming ability of NiMnPSi alloys Critical Rod Sample Composition Diameter [mm] 1 Ni.sub.77Mn.sub.3.5P.sub.18Si.sub.1.5 1 2 Ni.sub.75.5Mn.sub.5P.sub.18Si.sub.1.5 1 3 Ni.sub.74.5Mn.sub.6P.sub.18Si.sub.1.5 2 4 Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 3 5 Ni.sub.73.5Mn.sub.7P.sub.18Si.sub.1.5 2 6 Ni.sub.72.5Mn.sub.8P.sub.18Si.sub.1.5 1

(45) Sample metallic glasses (Samples 4 and 7-13) showing the effect of substituting P with Si, according to the formula Ni.sub.74Mn.sub.6.5P.sub.19.5-xSi.sub.x, in accordance with embodiments of the disclosure, are presented in Table 2 and FIG. 3. As shown, when the Si atomic concentration x is between 0.25 and 3.5 percent, the critical rod diameter is at least 1 mm. When the Si atomic concentration x is between 1 and 2 percent, the critical rod diameter is 2 to 3 mm. Differential calorimetry scans for several sample amorphous alloys, in accordance with embodiments of the disclosure, in which P is substituted with Si are presented in FIG. 4.

(46) TABLE-US-00002 TABLE 2 Sample alloys demonstrating the effect of increasing the Si atomic concentration at the expense of P on the glass-forming ability of NiMnPSi Alloys Critical Rod Sample Composition Diameter [mm] 7 Ni.sub.74Mn.sub.6.5P.sub.19Si.sub.0.5 1 8 Ni.sub.74Mn.sub.6.5P.sub.18.5Si.sub.1 1 9 Ni.sub.74Mn.sub.6.5P.sub.18.25Si.sub.1.25 2 4 Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 3 10 Ni.sub.74Mn.sub.6.5P.sub.17.75Si.sub.1.75 2 11 Ni.sub.74Mn.sub.6.5P.sub.17.5Si.sub.2 1 12 Ni.sub.74Mn.sub.6.5P.sub.17Si.sub.2.5 1 13 Ni.sub.74Mn.sub.6.5P.sub.16.5Si.sub.3 1

(47) Sample amorphous alloys (Samples 4 and 14-20), in accordance with embodiments of the disclosure, showing the effect of varying the metal to metalloid ratio, according to the formula (Ni.sub.0.919Mn.sub.0.081).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x, are presented in Table 3 and FIG. 5. As shown, when the metalloid atomic concentration is between 17 and 21.5 percent, the critical rod diameter is at least 1 mm. When the metalloid atomic concentration x is between 18.75 and 19.5, the critical rod diameter ranges from 2 to 3 mm. Differential calorimetry scans for several sample amorphous alloys, in accordance with embodiments of the disclosure, in which the metal to metalloid ratio is varied are presented in FIG. 6.

(48) TABLE-US-00003 TABLE 3 Sample amorphous alloys demonstrating the effect of increasing the total metalloid concentration at the expense of metals on the glass-forming ability of NiMnPSi alloys Critical Rod Sample Composition Diameter [mm] 14 Ni.sub.75.38Mn.sub.6.62P.sub.16.16Si.sub.1.34 1 15 Ni.sub.75.38Mn.sub.6.62P.sub.16.62Si.sub.1.38 1 16 Ni.sub.74.92Mn.sub.6.58P.sub.17.08Si.sub.1.42 1 17 Ni.sub.74.46Mn.sub.6.54P.sub.17.54Si.sub.1.46 2 4 Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 3 18 Ni.sub.73.54Mn.sub.6.46P.sub.18.46Si.sub.1.54 2 19 Ni.sub.73.08Mn.sub.6.42P.sub.18.92Si.sub.1.58 1 20 Ni.sub.72.62Mn.sub.6.38P.sub.19.38Si.sub.1.62 1

(49) An image of a 3 mm metallic glass rod, in accordance with embodiments of the disclosure, of example alloy Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 is presented in FIG. 7. An x-ray diffractogram verifying the amorphous structure of a 3 mm metallic glass rod of example alloy Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 is shown in FIG. 8.

(50) Lastly, the metallic glasses according to the disclosure exhibit a remarkable bending ductility. Specifically, under an applied bending load, the metallic glasses are capable of undergoing plastic bending in the absence of fracture for diameters up to at least 1 mm. Optical images of amorphous plastically bent rods at 1 mm diameter section of sample metallic glass Ni.sub.74Mn.sub.6.5P.sub.18Si.sub.1.5 are presented in FIG. 9.

Example Alloy System 2: NiMoNbMnPSi

(51) In one embodiment of the disclosure, Ni-based alloys with a Mo content of between 0.5 and 4 atomic percent, a Nb content of between 2 and 5.5 atomic percent, a Mn content of between 0.25 and 5 atomic percent, a P content of between 16 and 21 atomic percent, and a Si content of between 0.5 and 3 atomic percent have a critical rod diameter of at least 1 mm. In another embodiment, Ni-based alloys with a Mo content of between 2 and 3 atomic percent, a Nb content of between 3 and 4 atomic percent, a Mn content of between 1 and 2 atomic percent, a P content of between 17 and 19 atomic percent, and a Si content of between 1 and 2 atomic percent have a critical rod diameter of at least 5 mm or larger.

(52) Sample metallic glasses (Samples 21-29) showing the effect of substituting Mo with Mn, according to the formula Ni.sub.72.5-xMo.sub.4-xNb.sub.4Mn.sub.xP.sub.18Si.sub.1.5, are presented in Table 4 and FIG. 10. As shown, when the Mn atomic concentration x is between 0.25 and 5 percent, the critical rod diameter is at least 1 mm. When the Mn atomic concentration x is between 0.5 and 4 percent, the critical rod diameter is at least 2 mm, and when the Mn atomic concentration x is between 1 and 3.5 percent, the critical rod diameter is at least 3 mm. Differential calorimetry scans for sample metallic glasses in which Mo is substituted with Mn are presented in FIG. 11.

(53) TABLE-US-00004 TABLE 4 Sample metallic glasses demonstrating the effect of increasing the Mn atomic concentration at the expense of Mo on the glass-forming ability of NiMoNbMnPSi alloys Critical Rod Sample Composition Diameter [mm] 21 Ni.sub.72.5Mo.sub.4Nb.sub.4P.sub.18Si.sub.1.5 1 22 Ni.sub.72.5Mo.sub.3.5Nb.sub.4Mn.sub.0.5P.sub.18Si.sub.1.5 2 23 Ni.sub.72.5Mo.sub.3Nb.sub.4Mn.sub.1P.sub.18Si.sub.1.5 3 24 Ni.sub.72.5Mo.sub.2.5Nb.sub.4Mn.sub.1.5P.sub.18Si.sub.1.5 3 25 Ni.sub.72.5Mo.sub.2Nb.sub.4Mn.sub.2P.sub.18Si.sub.1.5 4 26 Ni.sub.72.5Mo.sub.1.5Nb.sub.4Mn.sub.2.5P.sub.18Si.sub.1.5 3 27 Ni.sub.72.5Mo.sub.1Nb.sub.4Mn.sub.3P.sub.18Si.sub.1.5 4 28 Ni.sub.72.5Mo.sub.0.5Nb.sub.4Mn.sub.3.5P.sub.18Si.sub.1.5 3 29 Ni.sub.72.5Nb.sub.4Mn.sub.4P.sub.18Si.sub.1.5 2

(54) Sample metallic glasses, in accordance with embodiments of the disclosure, (Samples 25 and 30-34) showing the effect of substituting Ni with Mn, according to the formula Ni.sub.74.5-xMo.sub.2.5Nb.sub.3.5Mn.sub.xP.sub.18Si.sub.1.5, are presented in Table 5 and FIG. 12. As shown, when the Mn atomic concentration x is between 0 and 4 percent, the critical rod diameter is at least 1 mm. When the Mn atomic concentration x is at between 0.5 and 3.5 percent, the critical rod diameter is at least 2 mm, and when the Mn atomic concentration x is between 1 and 2.75 percent, the critical rod diameter is at least 4 mm. Differential calorimetry scans for sample metallic glasses in which Ni is substituted with Mn are presented in FIG. 13.

(55) TABLE-US-00005 TABLE 5 Sample metallic glasses demonstrating the effect of increasing the Mo atomic concentration at the expense of Nb on the glass-forming ability of NiMoNbMnPSi alloys Critical Rod Sample Composition Diameter [mm] 30 Ni.sub.72.5Mo.sub.1Nb.sub.5Mn.sub.2P.sub.18Si.sub.1.5 1 31 Ni.sub.72.5Mo.sub.1.5Nb.sub.4.5Mn.sub.2P.sub.18Si.sub.1.5 3 25 Ni.sub.72.5Mo.sub.2Nb.sub.4Mn.sub.2P.sub.18Si.sub.1.5 4 32 Ni.sub.72.5Mo.sub.2.5Nb.sub.3.5Mn.sub.2P.sub.18Si.sub.1.5 4 33 Ni.sub.72.5Mo.sub.3Nb.sub.3Mn.sub.2P.sub.18Si.sub.1.5 3 34 Ni.sub.72.5Mo.sub.3.5Nb.sub.2.5Mn.sub.2P.sub.18Si.sub.1.5 1

(56) Sample metallic glasses, in accordance embodiments of the disclosure, (Samples 32 and 35-41) showing the effect of substituting Nb with Mo, according to the formula Ni.sub.72.5-xMo.sub.xNb.sub.6-xMn.sub.2P.sub.18Si.sub.1.5, are presented in Table 6 and FIG. 14. As shown, when the Mo atomic concentration x is between 1 and 3.5 percent, the critical rod diameter is at least 1 mm. When the Mo atomic concentration x is at between 1.5 and 3 percent, the critical rod diameter is at least 3 mm, and when the Mn atomic concentration x is between 2 and 2.5 percent, the critical rod diameter is at least 4 mm. Differential calorimetry scans for sample metallic glasses in which Nb is substituted with Mo are presented in FIG. 15.

(57) TABLE-US-00006 TABLE 6 Sample metallic glasses demonstrating the effect of increasing the Mn atomic concentration at the expense of Ni on the glass-forming ability of NiMoNbMnPSi alloys Critical Rod Sample Composition Diameter [mm] 35 Ni.sub.74.5Mo.sub.2.5Nb.sub.3.5P.sub.18Si.sub.1.5 1 36 Ni.sub.74Mo.sub.2.5Nb.sub.3.5Mn.sub.0.5P.sub.18Si.sub.1.5 2 37 Ni.sub.73.5Mo.sub.2.5Nb.sub.3.5Mn.sub.1P.sub.18Si.sub.1.5 5 38 Ni.sub.73Mo.sub.2.5Nb.sub.3.5Mn.sub.1.5P.sub.18Si.sub.1.5 5 32 Ni.sub.72.5Mo.sub.2.5Nb.sub.3.5Mn.sub.2P.sub.18Si.sub.1.5 4 39 Ni.sub.72Mo.sub.2.5Nb.sub.3.5Mn.sub.2.5P.sub.18Si.sub.1.5 5 40 Ni.sub.71.5Mo.sub.2.5Nb.sub.3.5Mn.sub.3P.sub.18Si.sub.1.5 2 41 Ni.sub.71Mo.sub.2.5Nb.sub.3.5Mn.sub.3.5P.sub.18Si.sub.1.5 2

(58) An image of a 5 mm metallic glass rod of example alloy Ni.sub.73Mo.sub.2.5Nb.sub.3.5Mn.sub.1.5P.sub.18Si.sub.1.5 is presented in FIG. 16. An x-ray diffractogram verifying the amorphous structure of a 5 mm metallic glass rod of example alloy Ni.sub.73Mo.sub.2.5Nb.sub.3.5Mn.sub.1.5P.sub.18Si.sub.1.5 is shown in FIG. 17.

Example Alloy System 3: NiCrMnPSi

(59) The alloys according to embodiments of the disclosure may demonstrate high-glass-forming ability. In some embodiments of the disclosure, Ni-based alloys with a Cr content of between 5 and 15 atomic percent, a Mn content of between 1 and 7 atomic percent, a P content of between 16 and 21 atomic percent, and a Si content of between 0.5 and 3 atomic percent have a critical rod diameter of at least 1 mm. In other embodiments, Ni-based alloys with a Cr content of between 8 and 10 atomic percent, a Mn content of between 2 and 5 atomic percent, a P content of between 17 and 19 atomic percent, and a Si content of between 1 and 2 atomic percent a critical rod diameter of at least 4 mm.

(60) The alloys according to embodiments of the disclosure may also demonstrate a high stability of the supercooled liquid against crystallization, T. In some embodiments of the disclosure, Ni-based alloys with a Cr content of between 6 and 15 atomic percent, a Mn content of between 0.25 and 6 atomic percent, a combined P and Si content of between 18 and 21 atomic percent, and a Si content of between 0.5 and 4 atomic percent have a stability of the supercooled liquid against crystallization T of at least 50 C. In other embodiments, Ni-based alloys with a Cr content of between 8 and 11 atomic percent, a Mn content of between 2 and 3.5 atomic percent, a combined P and Si content of between 18.5 and 19.5 atomic percent, and a Si content of between 0.25 and 1.5 atomic percent have a stability of the supercooled liquid against crystallization T of at least 62.5 C.

(61) Sample metallic glasses (Samples 42-51) showing the effect of substituting Ni with Cr, according to the formula Ni.sub.77.5-xCr.sub.xMn.sub.3P.sub.18Si.sub.1.5, are presented in Table 7 and FIG. 18. As shown, when the Cr atomic concentration x is between 5 and 15 percent, the critical rod diameter is at least 1 mm; when the Cr atomic concentration x is between 6 and 13 percent, the critical rod diameter is at least 2 mm; when the Cr atomic concentration x is between 7 and 11 percent, the critical rod diameter is at least 3 mm; and when the Cr atomic concentration x is between 8 and 10 percent, the critical rod diameter is at least 4 mm.

(62) TABLE-US-00007 TABLE 7 Sample metallic glasses demonstrating the effect of increasing the Cr atomic concentration at the expense of NI on the glass-forming ability of NiCrMnPSi alloys Critical Rod Sample Composition Diameter [mm] 42 Ni.sub.71.5Cr.sub.6Mn.sub.3P.sub.18Si.sub.1.5 1 43 Ni.sub.70.5Cr.sub.7Mn.sub.3P.sub.18Si.sub.1.5 2 44 Ni.sub.69Cr.sub.8.5Mn.sub.3P.sub.18Si.sub.1.5 3 45 Ni.sub.68.5Cr.sub.9Mn.sub.3P.sub.18Si.sub.1.5 3 46 Ni.sub.68Cr.sub.9.5Mn.sub.3P.sub.18Si.sub.1.5 4 47 Ni.sub.67.5Cr.sub.10Mn.sub.3P.sub.18Si.sub.1.5 3 48 Ni.sub.66.5Cr.sub.11Mn.sub.3P.sub.18Si.sub.1.5 2 49 Ni.sub.65.5Cr.sub.12Mn.sub.3P.sub.18Si.sub.1.5 2 50 Ni.sub.64.5Cr.sub.13Mn.sub.3P.sub.18Si.sub.1.5 1 51 Ni.sub.63.5Cr.sub.14Mn.sub.3P.sub.18Si.sub.1.5 1

(63) Sample metallic glasses (Samples 46 and 52-60) showing the effect of substituting Ni with Mn, according to the formula Ni.sub.71-xCr.sub.9.5Mn.sub.xP.sub.18Si.sub.1.5, are presented in Table 8 and FIG. 19. As shown, when the Mn atomic concentration x is between 1 and 7 percent, the critical rod diameter is at least 1 mm; when the Mn atomic concentration x is between 2 and 6 percent, the critical rod diameter is at least 2 mm; when the Mn atomic concentration x is between 2 and 5.5 percent, the critical rod diameter is at least 3 mm; and when the Mn atomic concentration x is between 2 and 5 percent, the critical rod diameter is at least 4 mm.

(64) TABLE-US-00008 TABLE 8 Sample metallic glasses demonstrating the effect of increasing the Mn atomic concentration at the expense of NI on the glass-forming ability of NiCrMnPSi alloys Critical Rod Sample Composition Diameter [mm] 52 Ni.sub.69.5Cr.sub.9.5Mn.sub.1.5P.sub.18Si.sub.1.5 1 53 Ni.sub.69Cr.sub.9.5Mn.sub.2P.sub.18Si.sub.1.5 1 54 Ni.sub.68.5Cr.sub.9.5Mn.sub.2.5P.sub.18Si.sub.1.5 4 46 Ni.sub.68Cr.sub.9.5Mn.sub.3P.sub.18Si.sub.1.5 4 55 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18Si.sub.1.5 5 56 Ni.sub.67Cr.sub.9.5Mn.sub.4P.sub.18Si.sub.1.5 3 57 Ni.sub.66.5Cr.sub.9.5Mn.sub.4.5P.sub.18Si.sub.1.5 4 58 Ni.sub.66Cr.sub.9.5Mn.sub.5P.sub.18Si.sub.1.5 2 59 Ni.sub.65.5Cr.sub.9.5Mn.sub.5.5P.sub.18Si.sub.1.5 2 60 Ni.sub.65Cr.sub.9.5Mn.sub.6P.sub.18Si.sub.1.5 1

(65) Sample metallic glasses (Samples 55 and 61-65) showing the effect of substituting P with Si, according to the formula Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19.5-xSi.sub.x, are presented in Table 9 and FIG. 20. As shown, when the Si atomic concentration x is between 0.25 and 3 percent, the critical rod diameter is at least 1 mm; when the Si atomic concentration x is between 1 and 2.5 percent, the critical rod diameter is at least 2 mm; when the Si atomic concentration x is between 1 and 2.25 percent, the critical rod diameter is at least 3 mm; and when the Si atomic concentration x is between 1 and 2 percent, the critical rod diameter is at least 4 mm.

(66) TABLE-US-00009 TABLE 9 Sample metallic glasses demonstrating the effect of increasing the Si atomic concentration at the expense of P on the glass-forming ability of NiCrMnPSi alloys Critical Rod Sample Composition Diameter [mm] 61 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19Si.sub.0.5 1 62 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18.5Si.sub.1 1 55 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18Si.sub.1.5 5 63 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.17.5Si.sub.2 3 64 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.17Si.sub.2.5 2 65 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.16.5Si.sub.3 1

(67) Sample metallic glasses (Samples 55 and 66-75) showing the effect of increasing the total metalloid concentration at the expense of metals, according to the formula (Ni.sub.0.839Cr.sub.0.118Mn.sub.0.043).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x, are presented in Table 10 and FIG. 21. As shown, when the metalloids atomic concentration x is between 17 and 22 percent, the critical rod diameter is at least 1 mm; when the metalloids atomic concentration x is between 17.25 and 21.25 percent, the critical rod diameter is at least 2 mm; when the metalloids atomic concentration x is between 18.25 and 20.75 percent, the critical rod diameter is at least 3 mm; when the metalloids atomic concentration x is between 18.75 and 20.25 percent, the critical rod diameter is at least 4 mm; and when the metalloids atomic concentration x is between 19 and 20 percent, the critical rod diameter is at least 5 mm.

(68) TABLE-US-00010 TABLE 10 Sample amorphous alloys demonstrating the effect of increasing the total metalloid concentration at the expense of metals on the glass-forming ability of the NiCrMnPSi system Critical Rod Sample Composition Diameter [mm] 66 Ni.sub.69.18Cr.sub.9.74Mn.sub.3.58P.sub.16.15Si.sub.1.35 1 67 Ni.sub.68.76Cr.sub.9.68Mn.sub.3.56P.sub.16.62Si.sub.1.38 2 68 Ni.sub.68.34Cr.sub.9.62Mn.sub.3.54P.sub.17.08Si.sub.1.42 3 69 Ni.sub.67.92Cr.sub.9.56Mn.sub.3.52P.sub.17.54Si.sub.1.46 4 70 Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 5 55 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18Si.sub.1.5 5 71 Ni.sub.67.29Cr.sub.9.47Mn.sub.3.49P.sub.18.23Si.sub.1.52 5 72 Ni.sub.67.08Cr.sub.9.44Mn.sub.3.48P.sub.18.46Si.sub.1.54 4 73 Ni.sub.66.66Cr.sub.9.38Mn.sub.3.46P.sub.18.92Si.sub.1.58 3 74 Ni.sub.66.24Cr.sub.9.32Mn.sub.3.44P.sub.19.38Si.sub.1.62 2 75 Ni.sub.65.82Cr.sub.9.26Mn.sub.3.42P.sub.19.85Si.sub.1.65 1

(69) Differential calorimetry scans for sample metallic glasses in which Ni is substituted with Cr according to the formula Ni.sub.77.5-xCr.sub.xMn.sub.3P.sub.18Si.sub.1.5 are presented in FIG. 22. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g, solidus temperature T.sub.s, and liquidus temperature T.sub.l for sample alloys metallic glasses according to the formula Ni.sub.77.5-xCr.sub.xMn.sub.3P.sub.18Si.sub.1.5 are listed in Table 11. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g for sample metallic glasses according to the formula Ni.sub.77.5-xCr.sub.xMn.sub.3P.sub.18Si.sub.1.5 are plotted in FIG. 23. As shown, when the Cr atomic concentration x is between 6 and 15 percent, T is at least 50 C.; when the Cr atomic concentration x is between 7 and 12 percent, T is at least 55 C.; when the Cr atomic concentration x is between 7.5 and 11.5 percent, T is at least 60 C.; and when the Cr atomic concentration x is between 8 and 11 percent, T is at least 62.5 C.

(70) TABLE-US-00011 TABLE 11 Effect of increasing the Cr atomic concentration at the expense of Ni on the glass-transition, crystallization, T.sub.x (=T.sub.x T.sub.g), solidus, and liquidus temperatures of NiCrMnPSi alloys Sample Composition T.sub.g ( C.) T.sub.x ( C.) T.sub.x ( C.) T.sub.s ( C.) T.sub.l ( C.) 42 Ni.sub.71.5Cr.sub.6Mn.sub.3P.sub.18Si.sub.1.5 368.8 416.9 48.1 835.7 871.7 43 Ni.sub.70.5Cr.sub.7Mn.sub.3P.sub.18Si.sub.1.5 375.3 432.1 56.8 832.6 877.7 44 Ni.sub.69Cr.sub.8.5Mn.sub.3P.sub.18Si.sub.1.5 378.8 442.3 63.5 833.2 877.4 46 Ni.sub.68Cr.sub.9.5Mn.sub.3P.sub.18Si.sub.1.5 379.7 444.7 65.0 831.5 878.0 47 Ni.sub.67.5Cr.sub.10Mn.sub.3P.sub.18Si.sub.1.5 381.5 447.1 65.6 834.3 877.8 48 Ni.sub.66.5Cr.sub.11Mn.sub.3P.sub.18Si.sub.1.5 382.6 444.6 62.0 832.4 883.6 49 Ni.sub.65.5Cr.sub.12Mn.sub.3P.sub.18Si.sub.1.5 389.3 442.0 52.7 831.8 888.8 50 Ni.sub.64.5Cr.sub.13Mn.sub.3P.sub.18Si.sub.1.5 388.0 439.3 51.3 833.0 882.0

(71) Differential calorimetry scans for sample metallic glasses in which Ni is substituted with Mn according to the formula Ni.sub.71-xCr.sub.9.5Mn.sub.xP.sub.18Si.sub.1.5 are presented in FIG. 24. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g, solidus temperature T.sub.s, and liquidus temperature T.sub.l for sample alloys metallic glasses according to the formula Ni.sub.71-xCr.sub.9.5Mn.sub.xP.sub.18Si.sub.1.5 are listed in Table 12. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g for sample metallic glasses according to the formula Ni.sub.71-xCr.sub.9.5Mn.sub.xP.sub.18Si.sub.1.5 are plotted in FIG. 25. As shown, when the Mn atomic concentration x is between 1 and 6 percent, T is at least 50 C.; when the Mn atomic concentration x is between 2 and 5 percent, T is at least 55 C.; when the Mn atomic concentration x is between 2 and 4 percent, T is at least 60 C.; and when the Mn atomic concentration x is between 2 and 3.5 percent, T is at least 62.5 C.

(72) TABLE-US-00012 TABLE 12 Effect of increasing the Mn atomic concentration at the expense of Ni on the glass-transition, crystallization, T.sub.x (=T.sub.x T.sub.g), solidus, and liquidus temperatures of NiCrMnPSi alloys Sample Composition T.sub.g ( C.) T.sub.x ( C.) T.sub.x ( C.) T.sub.s ( C.) T.sub.l ( C.) 53 Ni.sub.69Cr.sub.9.5Mn.sub.2P.sub.18Si.sub.1.5 373.4 434.0 60.6 840.1 878.4 46 Ni.sub.68Cr.sub.9.5Mn.sub.3P.sub.18Si.sub.1.5 379.7 444.7 65.0 831.5 878.0 55 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18Si.sub.1.5 384.4 445.5 61.1 830.3 881.2 57 Ni.sub.66.5Cr.sub.9.5Mn.sub.4.5P.sub.18Si.sub.1.5 387.2 444.8 57.6 829.8 879.5 59 Ni.sub.65.5Cr.sub.9.5Mn.sub.5.5P.sub.18Si.sub.1.5 394.5 444.3 49.8 828.8 881.8

(73) Differential calorimetry scans for sample metallic glasses in which P is substituted with Si according to the formula Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19.5-xSi.sub.x are presented in FIG. 26. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g, solidus temperature T.sub.s, and liquidus temperature T.sub.l for sample alloys metallic glasses according to the formula Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19.4-xSi.sub.x are listed in Table 13. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g for sample metallic glasses according to the formula Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.19.5-xSi.sub.x are plotted in FIG. 27. As shown, when the Si atomic concentration x is between 0.25 and 3 percent, T is at least 55 C.; when the Si atomic concentration x is between 1 and 2.5 percent, T is at least 57.5 C.; when the Si atomic concentration x is between 1 and 2 percent, T is at least 60 C.; and when the Si atomic concentration x is between 1 and 1.5 percent, T is at least 62.5 C.

(74) TABLE-US-00013 TABLE 13 Effect of increasing the Si atomic concentration at the expense of P on the glass-transition, crystallization, T.sub.x (=T.sub.x T.sub.g), solidus, and liquidus temperatures of NiCrMnPSi alloys Sample Composition T.sub.g ( C.) T.sub.x ( C.) T.sub.x ( C.) T.sub.s ( C.) T.sub.l ( C.) 62 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18.5Si.sub.1 381.3 445.7 64.4 831.2 884.9 55 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18Si.sub.1.5 384.4 445.5 61.1 830.3 881.2 63 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.17.5Si.sub.2 383.0 445.0 62.0 831.6 870.7 64 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.17Si.sub.2.5 384.8 443.2 58.4 830.3 868.0

(75) Differential calorimetry scans for sample metallic glasses in which the total metalloid concentration is increased at the expense of metals according to the formula (Ni.sub.0.839Cr.sub.0.118Mn.sub.0.043).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x are presented in FIG. 28. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g, solidus temperature T.sub.s, and liquidus temperature T.sub.l for sample alloys metallic glasses according to the formula Ni.sub.0.839Cr.sub.0.118Mn.sub.0.043).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x are listed in Table 14. The glass-transition temperature T.sub.g, crystallization temperature T.sub.x, and difference between glass-transition and crystallization temperatures T=T.sub.xT.sub.g for sample metallic glasses according to the formula Ni.sub.0.839Cr.sub.0.118Mn.sub.0.043).sub.100-x(P.sub.0.923Si.sub.0.077).sub.x are plotted in FIG. 29. As shown, when the metalloids atomic concentration x is greater than 18 percent and up to 21 percent, T is at least 50 C.; when the metalloids atomic concentration x is greater than 18 percent and up to 20.5 percent, T is at least 52.5 C.; when the metalloids atomic concentration x is between 18.25 and 20.25 percent, T is at least 57.5 C.; when the metalloids atomic concentration x is between 18.5 and 20 percent, T is at least 60 C.; and when the metalloids atomic concentration x is between 18.5 and 19.5 percent, T is at least 62.5 C.

(76) TABLE-US-00014 TABLE 14 Effect of increasing the total metalloid concentration at the expense of metals on the glass-transition, crystallization, T.sub.x (=T.sub.x T.sub.g), solidus, and liquidus temperatures of NiCrMnPSi alloys T.sub.x Sample Composition T.sub.g ( C.) T.sub.x ( C.) ( C.) T.sub.s ( C.) T.sub.l ( C.) 67 Ni.sub.68.76Cr.sub.9.68Mn.sub.3.56P.sub.16.62Si.sub.1.38 378.1 419.6 41.5 834.9 869.4 68 Ni.sub.68.34Cr.sub.9.62Mn.sub.3.54P.sub.17.08Si.sub.1.42 380.1 439.6 59.5 834.4 872.5 69 Ni.sub.67.92Cr.sub.9.56Mn.sub.3.52P.sub.17.54Si.sub.1.46 382.2 446.9 64.7 832.5 872.2 70 Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 386.5 449.4 62.9 831.7 881.9 55 Ni.sub.67.5Cr.sub.9.5Mn.sub.3.5P.sub.18Si.sub.1.5 384.4 445.5 61.1 830.3 881.2 72 Ni.sub.67.08Cr.sub.9.44Mn.sub.3.48P.sub.18.46Si.sub.1.54 386.2 444.6 58.4 829.8 881.9 73 Ni.sub.66.66Cr.sub.9.38Mn.sub.3.46P.sub.18.92Si.sub.1.58 393.6 444.7 51.1 830.4 897.4 74 Ni.sub.66.24Cr.sub.9.32Mn.sub.3.44P.sub.19.38Si.sub.1.62 396.8 443.6 46.8 830.3 877.2

(77) Among the alloy compositions investigated in this disclosure, one of the alloys exhibiting the highest glass-forming ability is Example 70, having composition Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48, which has critical rod diameter of 5 mm and stability of the supercooled liquid against crystallization T of 62.9 C. This alloy has a high notch toughness of 89.4 MPa m.sup.1/2 and a high yield strength of 2362 MPa. The measured notch toughness and yield strength of sample metallic glass Ni.sub.67.1Cr.sub.10Nb.sub.3.4P.sub.18Si.sub.1.5 are listed along with the critical rod diameter and stability of the supercooled liquid against crystallization in Table 15. An image of a 5 mm diameter amorphous Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 rod is shown in FIG. 30. An x-ray diffractogram taken on the cross section of a 5 mm diameter Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 rod verifying its amorphous structure is shown in FIG. 31. The stress-strain diagram for sample metallic glass Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 is presented in FIG. 32.

(78) TABLE-US-00015 TABLE 15 Critical rod diameter, notch toughness, and yield strength of metallic glass Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 Notch Critical Rod Toughness Yield Sample Composition Diameter [mm] T.sub.x ( C.) [MPa m.sup.1/2] Strength [MPa] 29 Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 5 62.9 89.4 1.8 2362

(79) Lastly, the alloys according to the disclosure exhibit a remarkable bending ductility. Specifically, under an applied bending load, the alloys are capable of undergoing plastic bending in the absence of fracture for diameters up to at least 1 mm. An image of a metallic glass rod of example metallic glass Ni.sub.67.71Cr.sub.9.53Mn.sub.3.51P.sub.17.77Si.sub.1.48 plastically bent at 1-mm diameter section is presented in FIG. 33.

(80) Description of Methods of Processing the Sample Alloys

(81) A method for producing the alloys involves inductive melting of the appropriate amounts of elemental constituents in a quartz tube under inert atmosphere. The purity levels of the constituent elements were as follows: Ni 99.995%, Cr 99.996%, Mn 99.9998%, Mo 99.95%, Nb 99.95%, P 99.9999%, and Si 99.9999%. Prior to producing an amorphous article from an alloy of the disclosure, the alloy ingots may be fluxed with a reducing agent such as boron oxide. A method for fluxing the alloy ingots involves re-melting the ingots in a quartz tube under inert atmosphere, bringing the alloy melt in contact with molten boron oxide and allowing the two melts to interact for about a time period of 1000 seconds at a temperature of about 1100 C. or higher, and subsequently water quenching. A method for producing metallic glass rods from the alloy ingots involves re-melting the ingots in quartz tubes of 0.5-mm thick walls in a furnace at 1100 C. or higher, and particularly between 1200 C. and 1400 C., under high purity argon and rapidly quenching in a room-temperature water bath.

(82) In general, amorphous articles from the alloy of the disclosure can be produced by (1) re-melting the alloy ingots in quartz tubes having 0.5-mm thick walls, holding the melt at a temperature of about 1100 C. or higher, and particularly between 1200 C. and 1400 C., under inert atmosphere, and rapidly quenching in a liquid bath; or (2) re-melting the alloy ingots, holding the melt at a temperature of about 1100 C. or higher, and particularly between 1200 C. and 1400 C., under inert atmosphere, and injecting or pouring the molten alloy into a metal mold, particularly made of copper, brass, or steel.

(83) Having described several embodiments, it will be recognized by those skilled in the art that various modifications, alternative constructions, and equivalents may be used without departing from the spirit of the disclosure. Those skilled in the art will appreciate that the presently disclosed embodiments teach by way of example and not by limitation. Therefore, the matter contained in the above description or shown in the accompanying drawings should be interpreted as illustrative and not in a limiting sense. Additionally, a number of well-known processes and elements have not been described in order to avoid unnecessarily obscuring the disclosure. The following claims are intended to cover all generic and specific features described herein, as well as all statements of the scope of the present method and system, which, as a matter of language, might be said to fall therebetween.

(84) Test Methodology for Measuring Notch Toughness

(85) The notch toughness of sample metallic glasses was performed on 3 mm diameter rods. The rods were notched using a wire saw with a root radius of between 0.10 and 0.13 m to a depth of approximately half the rod diameter. The notched specimens were placed on a 3-point bending fixture with span distance of 12.7 mm and carefully aligned with the notched side facing downward. The critical fracture load was measured by applying a monotonically increasing load at constant cross-head speed of 0.001 mm/s using a screw-driven testing frame. At least three tests were performed, and the variance between tests is included in the notch toughness plots. The stress intensity factor for the geometrical configuration employed here was evaluated using the analysis by Murakimi (Y. Murakami, Stress Intensity Factors Handbook, Vol. 2, Oxford: Pergamon Press, p. 666 (1987)).

(86) Test Methodology for Measuring Yield Strength

(87) Compression testing of exemplary metallic glasses was performed on cylindrical specimens 3 mm in diameter and 6 mm in length by applying a monotonically increasing load at constant cross-head speed of 0.001 mm/s using a screw-driven testing frame. The strain was measured using a linear variable differential transformer. The compressive yield strength was estimated using the 0.2% proof stress criterion.

(88) The alloys and metallic glasses described herein can be valuable in the fabrication of electronic devices. An electronic device herein can refer to any electronic device known in the art. For example, it can be a telephone, such as a mobile phone, and a landline phone, or any communication device, such as a smart phone, including, for example an iPhone, and an electronic email sending/receiving device. It can be a part of a display, such as a digital display, a TV monitor, an electronic-book reader, a portable web-browser (e.g., iPad), and a computer monitor. It can also be an entertainment device, including a portable DVD player, conventional DVD player, Blue-Ray disk player, video game console, music player, such as a portable music player (e.g., iPod), etc. It can also be a part of a device that provides control, such as controlling the streaming of images, videos, sounds (e.g., Apple TV), or it can be a remote control for an electronic device. It can be a part of a computer or its accessories, such as the hard drive tower housing or casing, laptop housing, laptop keyboard, laptop track pad, desktop keyboard, mouse, and speaker. The article can also be applied to a device such as a watch or a clock.

(89) Having described several embodiments, it will be recognized by those skilled in the art that various modifications, alternative constructions, and equivalents may be used without departing from the spirit of the disclosure. Additionally, a number of well-known processes and elements have not been described in order to avoid unnecessarily obscuring the disclosure. Accordingly, the above description should not be taken as limiting the scope of the disclosure.

(90) Those skilled in the art will appreciate that the presently disclosed embodiments teach by way of example and not by limitation. Therefore, the matter contained in the above description or shown in the accompanying drawings should be interpreted as illustrative and not in a limiting sense. The following claims are intended to cover all generic and specific features described herein, as well as all statements of the scope of the present method and system, which, as a matter of language, might be said to fall therebetween.