Alloy for producing bulk metallic glasses and shaped bodies therefrom

Abstract

The invention relates to an alloy having the following composition: NiaNi CuaCu NbbNb TabTa ZrcZr HfcHf TicTi FedFe CrdCr CodCo MndMn VeV MoeMo SnfSn AgfAg ZnfZn AlfAl SifSi GefGe SbfSb BgB CgC OhO HhH NhN Pi, with 30.00 wt.% ≤ aNi + aCu ≤ 55.00 wt.%, 35.00 wt.% ≤ bNb + bTa ≤ 68.00 wt.%, 0 wt.% ≤ cZr + cHf + cTi ≤ 12.50 wt.%, 0 wt.% ≤ dFe + dCr + dCo + dMn ≤ 8.50 wt.%, 0 wt.% ≤ eV + eMo ≤ 10.00 wt.%, 0 wt.% ≤ fSn + fAg + fZn + fAl + fSi + fGe + fSb ≤ 10.00 wt.%, 0 wt.% ≤ gB + gC ≤ 0.60 wt.%, 0 wt.% ≤ hO + hH + hN ≤ 0.10 wt.%, 0 wt.% < i ≤ 2.40 wt.%, wherein the sum of all wt.% aNi + aCu + bNb + bTa + cZr + cHf + cTi + dFe + dCr + dCo + dMn + eV + eMo + fSn + fAg + fZn + fAl + fSi + fGe + fSb + gB + gC + hO + hH + hN + i = 100 wt.% and the wt.% are each based on the total weight of the alloy, with the exception of the following alloys: Ni51,20Nb48,36P0,44, Ni51,65Nb47,47P0,88, Ni52,11Nb46,56P1,33, Ni47,58Nb50,22P2,20, Ni44,91Nb41,47Ta11,54P2,08, Ni42,52Nb33,66Ta21,85P1,97, Ni40,38Nb26,63Ta31,12P1,87, Ni36,68Nb14,51Ta47,11P1,70, Ni35,07Nb9,25Ta54,06P1,62, Ni33,59Nb4,43Ta60,42P1,56.

Description

[0001] Description: University of Saarland, 66123 Saarbrücken (Germany) “Alloy for the production of metallic solid glasses and shaped bodies therefrom” The invention relates to an alloy of the composition: Ni aNi Cu aCu Nb bNb Ta bTa Zr cZr Hf cHf Ti cTi Fe dFe Cr dCr Co dCo Mn dMn V eV Mon eMo Sn fSn Ag fAg Zn fZn Al fAl Si fSi Ge fGe Sb fSb B gB C gC O hO H hH N hN P i , with 30.00 wt.% ≤ a Ni + a Cu ≤ 55.00 wt%, 35.00 wt% ≤ b Nb + b Ta ≤ 68.00 wt%, 0 wt% ≤ c Zr + c Hf + c Ti ≤ 12.50% by weight, 0% by weight ≤ d Fe + d Cr + d Co + d Mn ≤ 8.50% by weight, 0% by weight ≤ eV + eMo ≤ 10.00% by weight, 0% by weight ≤ f Sn + f Ag + f Zn + fAl + f Si + f Ge + f Sb ≤ 10.00 wt%, 0 wt% ≤ g B + g C ≤ 0.60 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt%, 0 wt% < i ≤ 2.40 wt%, where the sum of all wt% a Ni + a Cu + b Nb + b Ta + c Zr + c Hf + c Ti + d Fe + d Cr + d Co + d Mn + e V + e Mo + f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb + g B + g C + h O + h H + h N + i = 100 wt.% and the wt.% are based on the total weight of the alloy, with the exception of the following alloys: Ni51.20Nb48.36P0.44, Ni51.65Nb47.47P0.88, Ni52.11Nb46.56P1.33, Ni47.58Nb50.22P2.20, Ni44.91Nb41.47Ta11.54P2.08, Ni 42,52 Nb 33,66 Ta 21,85 P 1,97 , Ni 40,38 Nb 26,63 Ta31,12 Q 1,87 , Ni 36,68 No 14,51 Dad 47,11 Q 1,70 , Ni 35,07 No 9,25 Dad 54,06 Q 1,62 , Ni 33,59 No 4,43 Dad 60,42 Q 1,56. The exceptions exclude from the scope of protection those alloys for which the inventors have determined properties that differ from neighboring alloy compositions, in particular mechanical properties or a lower glass-forming capacity. Furthermore, the invention relates to a shaped body produced from an alloy according to the invention, preferably by suction or pressure casting. An alloy according to the invention for producing metallic solid glasses and shaped bodies made therefrom solidify amorphously or at least partially amorphously, where partially amorphous in the sense of this invention means that a shaped body formed from the alloy is at least 50 vol.% amorphous. The determination of a volume fraction of a crystalline phase is described in EP 3444370 A1.The alloy according to the invention can be used to produce amorphous or partially amorphous shaped bodies, for example, components, that exhibit particularly good mechanical properties and, in particular, have a yield strength or fracture strength that is significantly higher than that of crystalline-solidifying metal alloys. A copper-based alloy for producing solid metallic glasses is known, for example, from EP 3444370 A1. Another amorphous-solidifying alloy is known from DE 102016008074 A1. Further alloys are known from JP 4346192 B2, US 4968363 A, JP S6233736 A, JP S63 297532 A, CN 108950309 A, CN 1982495 A, DE 2534379 A1 and WO 2004 / 009268 A2, as well as Kawashime A et al. “Highly corrosion-resistant Ni-based bulk amorphous alloys”, Materials Science, Elsevier, Amsterdam, NL, vol. 304-306, May 31, 2001, p. 753-757, ISSN 0921-5093.The invention is based on the object of creating an amorphous or partially amorphous solidifying alloy with the composition mentioned at the outset, which has particularly good mechanical properties and is particularly suitable for producing high-strength components such as gears for high-quality watches or medical instruments such as scalpels. Furthermore, the invention is based on the object of creating an amorphous or partially amorphous solidifying alloy based on nickel, niobium and phosphorus, which contains fewer components than known amorphous or at least partially amorphous solidifying alloys and which has page 2 / 17 comparable high mechanical properties as well as particularly good glass formation properties. According to the invention, the object is achieved by the features of claim 1. The elements hydrogen, oxygen and nitrogen are impurities which in total make up a weight fraction of up to 0.10 wt.-% may be contained in a Ni-Nb-P base alloy without reducing the glass-forming ability of the alloy. The order of the components of the alloys according to the subclaims corresponds to the order in which they are listed. This applies in particular to the optional features. For example, if a content of three components is specified as "X1 wt.%, X2 wt.%, preferably X." 2.1 % by weight, and X3% by weight”, the order is X1, then X2, followed by the restriction X 2.1 , then X3. It is advisable that 30.00 wt.% ≤ a Ni + a Cu ≤ 53.70 wt%, 35.00 wt% ≤ b Nb + b Ta ≤ 55.70% by weight, 0% by weight ≤ cZr + cHf + cTi ≤ 5.50% by weight, 0% by weight ≤ dFe + dCr + dCo + dMn ≤ 8.50% by weight, 0% by weight ≤ e V + e Mo ≤ 5.00% by weight, 0% by weight ≤ f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb ≤ 10.00 wt%, 0 wt% ≤ g B + gC ≤ 0.60 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt%, 0.10 wt% ≤ i ≤ 2.40 wt%, where the sum of all wt% a Ni + a Cu + b Nb + b Ta + c Zr + c Hf + c Ti + d Fe + d Cr + d Co + d Mn + e V + e Mo + f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb + g B + g C + hO + hH + hN + i = 100 wt.% and the wt.% are each based on the total weight of the alloy, with the exception of the following alloys: Ni 51,20 Nb 48,36 P 0,44 , Ni 51,65 Nb 47,47 P 0,88 , Ni 52,11 Nb 46,56 P 1,33 , Ni 47,58 Nb 50,22 P 2,20 , Ni 45,47 Nb 52,35 P 2,18 , Ni 44,91 N-b 41,47 Ta 11,54 P 2,08 , Ni 42,52 Nb 33,66 Ta 21,85 P1,97 , Ni 40,38 Nb 26,63 Ta 31,12 P 1,87 , Ni 36,68 Nb 14,51 Ta 47,11 P 1,70 , Ni 35,07 N-b 9,25 Ta 54,06 P 1,62 , Ni 33,59 Nb 4,43 Ta 60,42 P 1,56 . The inventors have found that an alloy of this composition (excluding Ni 45,47 Nb 52,35 P 2,18) has a special glass-forming ability which, in comparison to known alloys, is insensitive to reduced cooling rates during solidification. An alloy of this composition solidifies amorphous or partially amorphous, wherein partially amorphous in relation to this particularly preferred embodiment of the alloy means that a shaped body formed from the alloy is surprisingly at least 60 vol. % amorphous. Page 3 / 17 Surprisingly, it was also found that an alloy composition containing niobium bNb and tantalum bTa with bNb + bTa ≤ 55.70 wt. % has particularly good ductile properties and is therefore particularly suitable for the production of highly stressed components. For higher contents of niobium and tantalum, a particularly high hardness was determined, but severe embrittlement was observed. In one embodiment of the invention, 0 wt. % < i ≤ 1.40 wt. %, preferably 0.10 wt. % ≤ i ≤ 1.40 wt. %.The inventors have found that even with such a low phosphorus content, good glass-forming ability with high fracture strength can be achieved. To improve the glass-forming ability, a proportion of at least 0.10 wt.% phosphorus and a maximum of 1.40 wt.% is advantageous. An alloy of this composition can solidify amorphously or partially amorphously, where partially amorphous with regard to this particularly advantageous alloy means that a shaped body formed from the alloy is surprisingly at least 70 vol.% amorphous. Advantageously, 46.00 wt.% ≤ aNi + aCu ≤ 55.00 wt.%, 44.50 wt.% ≤ bNb + bTa ≤ 55.00 wt.%, 0 wt.% < i ≤ 1.40 wt.%, preferably 0.20 wt.% ≤ i ≤ 1.15 wt.%, c. Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = gB + g C = 0 wt% and 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, where a Cu = b Ta = 0 wt.%. Such an alloy consists exclusively of nickel, niobium, phosphorus, and up to 0.10 wt.% oxygen, hydrogen, and / or nitrogen, the latter three elements being impurities that may be contained, for example, in master alloys used to produce an alloy according to the invention. The inventors have surprisingly discovered that this alloy enables the production of a completely amorphous or partially amorphous molded body, where partially amorphous means that a molded body formed from the alloy is surprisingly at least 70 vol.% amorphous and also has a very high yield strength with a simultaneous large critical casting thickness D c of 5 mm. In one embodiment of the invention, 46.00 wt.% ≤ aNi + aCu ≤ 53.70 wt.%, 44.50 wt.% ≤ bNb + b Ta ≤ 52.50 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.20 wt% ≤ i ≤ 1.15 wt%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al Page 4 / 17 + f Si + f Ge + f Sb = g B + g C = 0 wt% and 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, where a Cu= bTa = 0 wt.%. Such an alloy consists exclusively of nickel, niobium, phosphorus, and up to 0.10 wt.% oxygen, hydrogen, and / or nitrogen, the latter three elements being impurities that may be contained, for example, in master alloys used to produce an alloy according to the invention. The inventors have found that this alloy enables the production of a completely amorphous or partially amorphous molded body, with very high fracture strength combined with a large critical casting thickness D c is achievable. Advantageously, 48.00 wt% ≤ aNi + aCu ≤ 49.00 wt%, 50.00 wt% ≤ bNb + bTa ≤ 51.00 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.60 wt% ≤ i ≤ 0.95 wt%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + fSi + f Ge + f Sb = g B + g C = 0 wt% and 0 wt% ≤ h O + h H + h N ≤ 0.10 wt% where 0 wt% < a Cu ≤ 9.00 wt.%, preferably 0.85 wt.% ≤ a Cu ≤ 8.95 wt%, and b Ta = 0 wt.%. The inventors have determined that a maximum phosphorus content of 1.40 wt.% and a copper content of up to 8.95 wt.% result in particularly high fracture strength and a large critical casting thickness of 5 mm. In one embodiment of the invention, 32.00 wt.% ≤ a Ni + a Cu ≤ 49.00 wt%, 51.00 wt% ≤ bNb + bTa ≤ 55.50 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.55 wt% ≤ i ≤ 0.95 wt%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = gB + g C = 0 wt% and 0 wt% ≤ h O + h H + h N ≤ 0.10 wt%, where 0 wt% < b Ta ≤ 55.50 wt.%, preferably 2.50 wt.% ≤ b Ta ≤ 55.50 wt% and a Cu = 0 wt.%. An alloy consisting of Ni, Nb, P, Ta and up to 0.10 wt.% impurities has a particularly high critical casting thickness D c of up to 6 mm, which gives this alloy a particularly high glass-forming ability, for example Ni 45,83 N-b 41,42 P 0,82 Ta 11,93 , where the index indicates the proportion of the respective element in wt.% based on the alloy weight and the sum of all wt.% is 100 wt.%. In a further embodiment of the invention, 37.00 wt.% ≤ a Ni + a Cu ≤ 47.00 wt%, 53.00 wt% ≤ b Nb + b Ta ≤ 63.00 wt.%, 0 wt.% ≤ i ≤ 1.40 wt.%, preferably 0.65 Page 5 / 17 wt.% ≤ i ≤ 0.82 wt.%, c Zr + c Hf + cTi = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + fSi + fGe + fSb = gB + gC = 0 wt% and 0 wt% ≤ hO + hH + hN ≤ 0.10 wt%, where 0 wt% < a Cu ≤ 3.50 wt.%, preferably 2.50 wt.% ≤ a Cu ≤ 3.50 wt%, and 11.75 wt% ≤ b Ta≤ 48.50 wt.%. The inventors have found that an alloy containing at least one of the elements phosphorus, tantalum, or copper, starting from the Ni-Nb base system, exhibits unexpectedly good glass-forming ability and particularly good mechanical properties even at low phosphorus contents of up to 0.10 wt.%. Furthermore, it has been found that the addition of tantalum and copper, even at low phosphorus contents and depending on the proportion of tantalum and copper, unexpectedly leads to an alloy with high fracture strength or high hardness. Such an alloy is advantageously suitable for a wide range of applications. 37.00 wt.% ≤ a Ni + a Cu ≤ 47.00 wt%, 53.00 wt% ≤ b Nb + b Ta ≤ 55.50 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.65 wt% ≤ i ≤ 0.82 wt%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = eV + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + gC = 0 wt% and 0 wt% ≤ hO + hH + hN ≤ 0.10 wt%, where 0 wt% < aCu ≤ 3.50 wt%, preferably 2.50 wt% ≤ a Cu ≤ 3.50 wt%, and 48.50 wt.%. The inventors have found that an alloy containing at least one of the elements tantalum or copper, starting from the Ni-Nb-P base system, continues to exhibit good glass-forming ability as well as particularly good mechanical properties. Furthermore, it was found that the addition of tantalum and copper unexpectedly leads to an alloy with high fracture strength, and it was determined that at b Nb + b Ta> 55.50 wt.%, a deterioration of ductile mechanical properties, in particular the yield strength and the fracture strength, occurs. Particularly good glass-forming ability combined with good mechanical properties was found up to a phosphorus content of 1.40 wt.%. In a further embodiment of the invention, 30.00 wt.% ≤ a Ni + a Cu ≤ 45.00 wt%, 53.00 wt% ≤ b Nb + b Ta ≤ 55.50 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.65 wt% ≤ i ≤ 0.85 wt%, 1.25 wt% ≤ dFe + dCr + dCo + dMn ≤ 7.85 wt%, cZr + cHf + c Ti = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C 0 wt%, 0 wt% ≤ h O + h H + Page 6 / 17 h N ≤ 0.10 wt%, 11.75 wt% ≤ b Ta ≤ 49.00 wt.%, wherein preferably d Fe = d Cr = dMn = aCu = 0 wt.%. Such an alloy according to the invention preferably consists of nickel, niobium, phosphorus, tantalum, and cobalt. The inventors have found that the combination of tantalum and cobalt added to a Ni-Nb-P base alloy has a positive effect on the hardness of the alloy. Particularly high Vickers hardnesses of > 900 HV5 (determination of Vickers hardness according to ISO 6507, as of July 2018) are advantageously achieved. Although the ductile properties decrease with increasing hardness, particularly hard alloy compositions are particularly well suited for tribological applications or applications in which components are subject to particularly high wear stresses. For example, an alloy according to the invention can be used to produce a guide rail of a honing device or as a component of a gear, for example a gear wheel of a transmission. In one embodiment of the invention, 46.00 wt.% ≤ a Ni + aCu ≤ 51.00 wt%, 38.00 wt% ≤ b Nb + b Ta ≤ 55.00 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.40 wt% ≤ i ≤ 2.15 wt%, 1.20 wt% ≤ cZr + cHf + cTi ≤ 5.00 wt%, 0 wt% ≤ hO + hH + h N ≤ 0.10 wt.%, and d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = 0 wt.%, preferably 1.20 wt.% ≤ c Zr ≤ 5.00 wt%, 2.50 wt% ≤ c Hf ≤ 5.00 wt%, 1.25 wt% ≤ c Ti ≤ 5.00 wt% and a Cu = b Ta= 0 wt.%. This embodiment relates to a Ni-Nb-P-based alloy that also contains up to 5.00 wt.% zirconium, hafnium, and / or titanium. Contrary to expectations, the addition of the latter three elements does not reduce the glass-forming ability and even leads to a high Vickers hardness (HV5 according to ISO 6507, as of July 2018). In one embodiment of the invention, 43.00 wt.% ≤ a Ni + a Cu ≤ 48.00 wt%, 50.00 wt% ≤ bNb + bTa ≤ 51.00 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.80 wt% ≤ i ≤ 0.90 wt%, particularly preferably i = 0.87 wt%, 0.50 wt% ≤ d Fe + d Cr + d Co + d Mn ≤ 5.00 wt.%, c Zr + c Hf + c Ti = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = 0 wt%, 0 wt% ≤ h O + h H + h N≤ to 0.10 wt.%, preferably a Cu = b Ta = 0 wt% and 1.50 wt% ≤ d Fe ≤ 4.75% by weight, 0.50% by weight ≤ d Cr ≤ 2.25% by weight, 1.50% by weight ≤ d Co ≤ 5.00 wt.%, 0.50 wt.% ≤ dMn ≤ 4.75 wt.%. Page 7 / 17 This embodiment relates to a Ni-Nb-P-based alloy that additionally contains iron, chromium, cobalt, and / or manganese. The addition of one of the last four elements surprisingly only slightly reduces the glass-forming ability and also leads to an alloy with high fracture strength, especially for i=0.87 wt.%. In a further embodiment of the invention, 48.00 wt.% ≤ a Ni + a Cu ≤ 51.00 wt%, 42.00 wt% ≤ bNb + bTa ≤ 50.00 wt%, 0 wt% < i ≤ 1.40 wt%, preferably 0.85 wt% ≤ i ≤ 0.95 wt%, 0.50 wt% ≤ e V + e Mo ≤ 8.50 wt.%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = fSn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = a Cu = b Ta = 0 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, preferably 0.50 wt.% ≤ e V ≤ 4.50% by weight, 1.25% by weight ≤ e Mo ≤ 8.10 wt.%. This embodiment of the invention relates to a Ni-Nb-P-based alloy that also contains vanadium and / or molybdenum. The inventors have found that the addition of vanadium and molybdenum only slightly influences the glass-forming properties and, in combination with phosphorus, results in particularly high fracture strength and a critical casting thickness D c from 3 to 5 mm. 48.00 wt.% ≤ a Ni + a Cu ≤ 51.00 wt%, 42.00 wt% ≤ b Nb + b Ta ≤ 50.00 wt.%, 0.10 wt.% ≤ i ≤ 1.40 wt.%, preferably 0.85 wt.% ≤ i ≤ 0.95 wt.%, 0.50 wt.% ≤ eV + e Mo ≤ 5.00 wt.%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = a Cu = b Ta = 0 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.20 wt.%, preferably 0.50 wt.% ≤ eV ≤ 4.50 wt.%, 1.25 wt.% ≤ eMo ≤ 4.50 wt.%. This embodiment of the invention relates to a Ni-Nb-P-based alloy which also contains vanadium and / or molybdenum. The addition of the latter two elements results in surprisingly good glass-forming ability and high fracture strength. In one embodiment of the invention, 46.00 wt.% ≤ a Ni + a Cu ≤ 49.00 wt%, 41.00 wt% ≤ b Nb + b Ta≤ 51.00 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.84 wt% ≤ i ≤ 0.89 wt%, 0.35 wt% ≤ f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb ≤ 10.00 wt.%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = g B + g C = a Cu = b Ta = 0 wt%, 0 wt% ≤ h O + hH + hN ≤ 0.10 wt.%, preferably 3.25 wt.% ≤ fSn ≤ 10.00 wt.%, 1.25 wt.% ≤ fAg ≤ 5.00 wt.%, 0.75 wt.% ≤ f Zn ≤ 3.00% by weight, 0.25% by weight ≤ f Al ≤ 1.25 wt.%, 0.25 Page 8 / 17 wt.% ≤ f Si ≤ 1.00% by weight, 0.75% by weight ≤ f Ge ≤ 2.75% by weight, 1.50% by weight ≤ f Sb≤ 5.25 wt.%. This embodiment relates to a Ni-Nb-P base alloy that also contains tin, silver, zinc, aluminum, silicon, germanium, and / or antimony. Contrary to expectations, the addition of one of the last seven elements does not negatively affect the glass-forming ability, but rather leads to surprisingly good glass-forming ability in the Ni-Nb-P base system. In a further embodiment of the invention, 48.00 wt.% ≤ a Ni + a Cu ≤ 49.00 wt%, 50.00 wt% ≤ b Nb + b Ta ≤ 51.00 wt.%, 0.10 wt.% ≤ i ≤ 1.40 wt.%, preferably 0.75 wt.% ≤ i ≤ 0.90 wt.%, preferably i = 0.87 wt.%, 0.10 wt.% ≤ g B + g C ≤ 0.60% by weight, cZr + cHf + cTi = dFe + dCr + dCo + dMn = eV + eMo = fSn + fAg + fZn + fAl + fSi + fGe + = a Cu = b Ta = 0 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt%, preferably 0.10 wt% ≤ g B≤ 0.50 wt%, 0.10 wt% ≤ g C ≤ 0.55 wt.%. This embodiment relates to a Ni-Nb-P-based alloy that also contains boron and / or carbon. Contrary to expectations, the inventors have found that boron and carbon in the stated amount do not alter the glass-forming ability of a Ni-Nb-P-based alloy. A critical casting thickness is expediently between 0.5 mm and 7.0 mm, i.e., 0.5 mm ≤ Dc ≤ 7.0 mm. The critical casting thickness D c is a technical measure of the glass-forming ability of an alloy. The greater the critical casting thickness, the greater the glass-forming ability of the alloy, i.e., its tendency toward amorphous or at least partially amorphous solidification. Determining the critical casting thickness D ccan be carried out as described in EP 3444370 A1. To determine the critical casting thickness Dc, several cylinders with a length of 50 mm and a diameter between 0.5 mm and 8 mm (in 0.5 mm or 1.0 mm increments) are cast. An XRD measuring surface is created on each of the cast cylinders by splitting the cylinder into two parts perpendicular to a cylinder axis outside the so-called heat-affected zone, for example, at 25 mm, i.e., in the middle. The critical casting thickness Dc is determined by an XRD measurement at the separation point across the entire cross-section. The solidification properties – amorphous, partially amorphous, or crystalline (page 9 / 17) – are determined on the samples with increasing diameter until the first of the samples is considered to have solidified into a crystalline state. The critical casting thickness D c is the diameter of the last sample that is considered amorphous or partially amorphous. The critical casting thickness D cis also a technical measure for the size of a molded body, for example, a component, that can be produced with the alloy and solidifies amorphously or partially amorphously despite its size. If a critical casting thickness for an alloy is, for example, 3 mm, the maximum size of a molded body produced from this alloy is smaller than the maximum size of a molded body produced from an alloy with a critical casting thickness D cof 5 mm. In an embodiment of the invention, the alloy has a Vickers hardness (HV5) between 840 and 1050. The Vickers hardness (HV5) is determined in accordance with ISO 6507 (as of July 2018). The hardness of an alloy according to the invention can advantageously be tailored to a high level and is suitable for many applications. In a further embodiment of the invention, the alloy has a fracture strength between 2.5 GPa and 5.5 GPa, with the fracture strength being determined in a 3-point bending test. An amorphous or partially amorphous solidifying alloy according to the invention is advantageously suitable for the production of high-strength components. Mechanical properties are a technical characteristic of an alloy and are suitable as a distinguishing feature for distinguishing one alloy from other alloys. The mechanical properties can be determined destructively or non-destructively on a test specimen.In one embodiment of the invention, the alloy has a yield strength between 4.40 GPa and 4.70 GPa, with the yield strength being determined in a 3-point bending test. For an alloy according to the invention, the yield strength is preferably between 4.40 GPa and 4.70 GPa, while the Vickers hardness (HV5) is between 850 and 930. An amorphous or partially amorphous solidifying alloy according to the invention is advantageously suitable for the production of high-strength, tribologically stressed components. Page 10 / 17 Fig. 9 shows a test setup for determining mechanical properties such as the yield strength s0.2% (0.2% means that a plastic strain is 0.2%), the elastic modulus E and the breaking strength in the three-point bending test. The test specimens 1 used to determine the breaking strength are cuboid-shaped with a width 2 of 2 mm (in Fig. 9 into the plane of the drawing), a height 3 of 1 mm and a length 4 of 20 mm.Two round supports 5 with a diameter dA of 5 mm are arranged at a distance 6 of 15 mm from each other. A specimen 1 is placed on the two supports 5 in such a way that specimen ends 7, i.e., end faces, are flush with the outer sides 8 of the supports 5. A compression member 9, through which a force F is applied, is cylindrical with a diameter dD of 5 mm and presses centrally on the cuboid-shaped specimen 1, i.e., a distance 10 from the center of the compression member 9 to the center of the supports 5 is equal and amounts to 7.5 mm. The compression member 9 moves at a speed of 0.3 mm / min. Further required test parameters for determining the ultimate strength are taken from ISO 7438 (as of October 2020).A standardized determination of the flexural strength of metallic materials, for example, according to ISO 7438 (as of October 2020), is not possible because the specimen dimensions required there are too large for a specimen made of an amorphous or semi-amorphous solidifying alloy. A molded article formed from an alloy according to the invention can be produced using the so-called suction casting process. For this purpose, the alloy, e.g., Ni, is cast into a molded article. 48,65 Nb 50,48 P 0,87, melted in an argon atmosphere using an arc and then sucked into a passively water-cooled copper mold by vacuum, the mold cavity of which represents the molded body to be produced, and removed after solidification. A particularly suitable die-casting production process is known from EP 3814034 A1. The invention is explained in more detail below with reference to exemplary embodiments and the attached drawings relating to exemplary embodiments. The index represents a proportion of the element in wt.% based on the total weight of the alloy, page 11 / 17 ie Ni 48,65 Nb 50,48 P 0,87 For example, it consists of 48.65 wt% Ni, 50.48 wt% Nb and 0.87 wt% P. Example 1 – Ni 48,65 Nb 50,48 P 0,87 : To produce 50 g of a high-purity Ni-P master alloy (Ni85.04 P14.96), 42.52 g of nickel and 7.48 g of phosphorus are inductively melted in an argon atmosphere in a quartz tube and homogenized for 5 minutes. After cooling to room temperature, the Ni-P master alloy produced in this way is used to produce the alloy Ni according to the invention. 48,65 Nb 50,48 P 0,87used as follows: To produce 16 g of the alloy Ni48.65Nb50.48P0.87, 6.9958 g of nickel, 8.0764 g of niobium, and 0.9278 g of the Ni85.04P14.96 master alloy are melted and mixed together in an arc under an argon atmosphere at 2000 °C. A shaped body with this alloy composition can be produced by suction casting or pressure casting according to EP 3814034 B1. A circular-cylindrical rod made from this alloy with a diameter of 5 mm has solidified amorphously. This is clearly demonstrated by an X-ray diffractogram (Cu-Ka radiation) determined on this rod, as shown in Fig. 1. In the three-point bending test, the alloy exhibits a modulus of elasticity of 143 GPa and a fracture strength of 4.7 GPa (see Fig. 3). Example 2 - Ni 45,83 Nb 41,42 Ta 11,93 P 0,82 : To produce 16 g of an inventive alloy Ni45.83Nb41.42Ta11.93P0.82, 6.5896 g of nickel, 6.6271 g of niobium, 1.9093 g of tantalum, and 0.8739 g of a Ni85.04P14.96 master alloy prepared according to Example 1 are melted and mixed together in an arc in an argon-protective atmosphere at 2000 °C. A shaped body with this alloy composition can be produced by suction casting or die casting according to EP 3814034 B1. Page 12 / 17 A circular-cylindrical rod made from this alloy with a diameter of 6 mm has solidified amorphously. This is clearly demonstrated by an X-ray diffractogram (Cu-Ka radiation) determined on this rod, as shown in Fig. 2. In the three-point bending test, the alloy exhibits a modulus of elasticity of 148 GPa and a fracture strength of 5.1 GPa (see Fig. 4). Fig. 5 shows Vickers hardness (HV5) of selected alloys according to the invention. Reference is now made to Fig.6a and 6b, which differ from those shown in Fig.3 and 4 in that the so-called yield strength (see 0,2% ) of the respective alloy. For an alloy with the composition Ni 48,65 Nb 50,48 P 0,87 4.4 GPa, while an alloy of composition Ni 45,83 Nb 41,42 Ta 11,93 P 0,82has a yield strength of 4.7 GPa. The yield strength was determined using a test setup shown in Fig. 9 on a specimen also shown in Fig. 9. Reference is now made to a diagram shown in Fig. 7, which shows the Vickers hardness (HV5) as well as the elastic modulus, the yield strength s0.2% and the fracture strength for various alloys. Fig. 7 differs from Fig. 5 by the addition of the fracture strength, yield strength and elastic modulus of the respective alloy. For alloys #20, #59, #60-62, a Vickers hardness (HV5) between 850 and 930 was determined, while the yield strength and fracture strength are particularly high between 4.5 GPa and 5.2 GPa. In addition, the elastic modulus increases from approximately 143 GPa to 148 GPa. For alloys #63-#69 and #84, the Vickers hardness (HV5) decreases from 920 to approximately 1.000, while the ultimate strength and yield strength decrease sharply from approximately 4 GPa to 2.5 GPa. The elastic modulus increases from approximately 148 GPa to 155 GPa. Surprisingly, the inventors discovered that at alloy composition #63, there is an inflection point, beyond which the Vickers hardness and elastic modulus continue to increase, while the yield strength and ultimate strength decrease, with yield strength and ultimate strength having identical values. The alloys with bNb+bTa ≤ 55.70 wt.% are advantageously particularly ductile, while alloys with a higher content are very brittle but very hard. The ductile alloys are particularly suitable for use as highly loaded gears in micromechanical systems or as particularly sharp and durable blades for cutting tools such as surgical instruments.Fig. 8 shows a compilation of mechanical properties of amorphous or partially amorphous solidifying alloys known from the prior art and alloys according to the invention. By adding phosphorus in a content of at least 0.10 wt.%, an improvement in the ductile properties can be achieved. By adding phosphorus and tantalum, a further increase in the ductile properties is possible. The numbering of the individual alloy compositions in Figs. 5, 7 and 8 refers to the examples of alloys according to the invention that solidify amorphously or at least partially amorphously, shown in the table below: Consecutive number # Alloy (subscript numerical value = proportion of the respective... 17 Ni 4887 Nb 4982 P 131 Page 15 / 17 61 Ni 4583 Nb 4142 Ta 1193 P 082 Page 16 / 17 101 Ni 4952 Nb 3967 Ti 893 P188 Page 17 / 17

Claims

Claims:

1. Alloy of composition: Ni aNi Cu aCu Nb bNb Ta bTa Zr cZr Hf cHf Ti cTi Fe dFe Cr dCr Co dCo Mn dMn V eV Mon eMo Sn fSn Ag fAg Zn fZn Al fAl Si fSi Ge fGe Sb fSb B gB C gC O hO H hH N hN P i , with 30.00 wt.% ≤ a Ni + a Cu ≤ 55.00 wt%, 35.00 wt% ≤ b Nb + b Ta ≤ 68.00% by weight, 0% by weight ≤ cZr + cHf + cTi ≤ 12.50% by weight, 0% by weight ≤ d Fe + d Cr + d Co + d Mn ≤ 8.50% by weight, 0% by weight ≤ e V + e Mo ≤ 10.00% by weight, 0% by weight ≤ f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb ≤ 10.00 wt%, 0 wt% ≤ g B + g C≤ 0.60 wt%, 0 wt% ≤ hO + hH + hN ≤ 0.10 wt%, 0 wt% < i ≤ 2.40 wt%, where the sum of all wt% a Ni + a Cu + b Nb + b Ta + c Zr + c Hf + c Ti + d Fe + d Cr + d Co + d Mn + e V + e Mo + f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb + g B + g C + h O + h H + h N + i = 100 wt.% and the wt.% are based on the total weight of the alloy, with the exception of the following alloys: Ni 51,20 Nb 48,36 P 0,44 , Ni 51,65 Nb 47,47 P 0,88 , Ni 52,11 Nb 46,56 P 1,33 , Ni 47,58 Nb 50,22 P 2,20 , Ni 44,91 Nb 41,47 Ta 11,54 P 2,08 , Ni 42,52 Nb 33,66 Ta 21,85 P 1,97 , Ni 40,38 Nb 26,63 Ta 31,12 P1,87 , Ni 36,68 Nb 14,51 Ta 47,11 P 1,70 , Ni 35,07 Nb 9,25 Ta 54,06 P 1,62 , Ni 33,59 Nb 4,43 Ta 60,42 P 1,56 2. Alloy according to claim 1, characterized in that 30.00 wt.% ≤ a Ni + a Cu ≤ 53.70% by weight, 35.00% by weight ≤ bNb + bTa ≤ 55.70% by weight, 0% by weight ≤ c Zr + c Hf + c Ti ≤ 5.50% by weight, 0% by weight ≤ d Fe + d Cr + d Co + d Mn ≤ 8.50% by weight, 0% by weight ≤ e V + e Mo ≤ 5.00% by weight, 0% by weight ≤ f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb ≤ 10.00 wt%, 0 wt% ≤ gB + gC ≤ 0.60 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, page 1 / 6 0.10 wt% ≤ i ≤ 2.40 wt%, where the sum of all wt% a Ni + a Cu + b Nb + b Ta + c Zr + c Hf + cTi + d Fe + d Cr + d Co + dMn + eV + eMo + fSn + fAg + fZn + fAl + fSi + fGe + fSb + gB + gC + hO + hH + hN + i = 100 wt.% and the wt.% are based on the total weight of the alloy, with the exception of the following alloys: Ni 51,20 Nb 48,36 P 0,44 , Ni 51,65 Nb 47,47 P 0,88 , Ni 52,11 Nb 46,56 P 1,33 , Ni 47,58 Nb 50,22 P 2,20 , Ni 45,47 Nb 52,35 P 2,18 , Ni 44,91 Nb 41,47 Ta 11,54 P 2,08 , Ni 42,52 Nb 33,66 Ta 21,85 P 1,97 , Ni 40,38 Nb 26,63 Ta 31,12 P 1,87 , Ni36.68Nb14.51Ta47.11P1.70, Ni35.07Nb9.25Ta54.06P1.62, Ni33.59Nb4.43Ta60.42P1.

56.

3. Alloy according to claim 1 or 2, characterized in that 0 wt.% < i ≤ 1.40 wt.%, preferably 0.10 wt.% ≤ i ≤ 1.40 wt.%.

4. Alloy according to claim 1, characterized in that 46.00 wt.% ≤ a Ni + aCu ≤ 55.00 wt%, 44.50 wt% ≤ b Nb + b Ta ≤ 55.00 wt.%, 0 wt.% < i ≤ 1.40 wt.%, preferably 0.20 wt.% ≤ i ≤ 1.15 wt.%, cZr + cHf + cTi = dFe + dCr + dCo + dMn = eV + eMo = fSn + fAg + fZn + fAl + fSi + fGe + f Sb = g B + g C = 0 wt% and 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, where a Cu = b Ta = 0 wt.%.

5. Alloy according to claim 1 or 2, characterized in that 46.00 wt.% ≤ a Ni + a Cu ≤ 53.70 wt%, 44.50 wt% ≤ b Nb + b Ta ≤ 52.50 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.20 wt% ≤ i ≤ 1.15 wt%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C= 0 wt% and 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, where a Cu = bTa = 0 wt.%.

6. Alloy according to claim 1 or 2, characterized in that 48.00 wt.% ≤ a Ni + a Cu ≤ 49.00 wt%, 50.00 wt% ≤ b Nb + b Ta ≤ 51.00 wt.%, 0.10 wt.% ≤ i ≤ 1.40 wt.%, preferably 0.60 wt.% ≤ i ≤ 0.95 wt.%, particularly preferably i = 0.87 wt.%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = 0 wt% and 0 wt% ≤ h O + h H + h N ≤ Page 2 / 6 0.10 wt%, where 0 wt% < a Cu ≤ 9.00 wt.%, preferably 0.85 wt.% ≤ a Cu ≤ 8.95 wt%, and b Ta= 0 wt.%.

7. Alloy according to claim 1 or 2, characterized in that 32.00 wt.% ≤ a Ni + a Cu ≤ 49.00 wt%, 51.00 wt% ≤ b Nb + b Ta ≤ 55.50 wt.%, 0.10 wt.% ≤ i ≤ 1.40 wt.%, preferably 0.55 wt.% ≤ i ≤ 0.95 wt.%, cZr + cHf + cTi = dFe + dCr + dCo + dMn = eV + eMo = fSn + fAg + fZn + fAl + fSi + fGe + f Sb = g B + g C = 0 wt% and 0 wt% ≤ h O + h H + h N ≤ 0.10 wt%, where 0 wt% < b Ta ≤ 55.00 wt.%, preferably 2.50 wt.% ≤ b Ta ≤ 55.00 wt.%, and a Cu = 0 wt.%.

8. Alloy according to claim 1, characterized in that 37.00 wt.% ≤ a Ni + a Cu ≤ 47.00 wt%, 53.00 wt% ≤ b Nb + b Ta ≤ 63.00 wt%, 0 wt% ≤ i ≤ 1.40 wt%, preferably 0.65 wt% ≤ i ≤ 0.82 wt%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn= e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + fSb = gB + gC = 0 wt% and 0 wt% ≤ hO + hH + hN ≤ 0.10 wt%, where 0 wt% < a Cu ≤ 3.50 wt.%, preferably 2.50 wt.% ≤ a Cu ≤ 3.50 wt%, and 11.75 wt% ≤ b Ta ≤ 48.50 wt.%.

9. Alloy according to claim 1 or 2, characterized in that 37.00 wt.% ≤ a Ni + a Cu ≤ 47.00 wt%, 53.00 wt% ≤ b Nb + b Ta ≤ 55.50 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.65 wt% ≤ i ≤ 0.82 wt%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = 0 wt% and 0 wt% ≤ h O + h H + h N≤ 0.10 wt.%, where 0 wt.% < aCu ≤ 3.50 wt.%, preferably 2.50 wt.% ≤ aCu ≤ 3.50 wt.%, and 11.75 wt.% ≤ b Ta ≤ 48.50 wt.%.

10. Alloy according to claim 1 or 2, characterized in that 30.00 wt.% ≤ aNi + aCu ≤ 45.00 wt.%, 53.00 wt.% ≤ bNb + bTa ≤ 55.50 wt.%, 0.10 wt.% ≤ i ≤ 1.40 wt.%, preferably 0.65 wt.% ≤ i ≤ 0.85 wt.%, 1.25 wt.% ≤ d Fe + d Cr + d Co + d Mn ≤ 7.85 wt.%, c Zr + c Hf + c Ti = e V + e Mo = f Sn + Page 3 / 6 f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C 0 wt%,0 wt% ≤ h O + h H + h N ≤ 0.10 wt%, 11.75 wt% ≤ b Ta ≤ 49.00 wt.%, wherein preferably d Fe = d Cr = d Mn = a Cu= 0 wt.%.

11. Alloy according to claim 1 or 2, characterized in that 46.00 wt.% ≤ a Ni + a Cu ≤ 51.00 wt%, 38.00 wt% ≤ b Nb + b Ta ≤ 55.00 wt%, 0.10 wt% ≤ i ≤ 1.40 wt%, preferably 0.40 wt% ≤ i ≤ 1.15 wt%, 1.20 wt% ≤ c Zr + c Hf + c Ti ≤ 5.00 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, and d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = 0 wt.%, preferably 1.20 wt.% ≤ c Zr ≤ 5.00 wt%, 2.50 wt% ≤ c Hf ≤ 5.00 wt%, 1.25 wt% ≤ c Ti ≤ 5.00 wt% and a Cu = b Ta = 0 wt.%.

12. Alloy according to claim 1 or 2, characterized in that 43.00 wt.% ≤ a Ni + a Cu≤ 48.00 wt%, 50.00 wt% ≤ b Nb + b Ta ≤ 51.00 wt.%, 0.10 wt.% ≤ i ≤ 1.40 wt.%, preferably 0.80 wt.% ≤ i ≤ 0.90 wt.%, particularly preferably i = 0.87 wt.%, 0.50 wt.% ≤ d Fe + d Cr + d Co + d Mn ≤ 8.00 wt.%, c Zr + c Hf + c Ti = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = 0 wt%, 0 wt% ≤ h O + h H + h N ≤ to 0.10 wt.%, preferably a Cu = b Ta = 0 wt% and 1.50 wt% ≤ d Fe ≤ 4.75% by weight, 0.50% by weight ≤ d Cr ≤ 2.25 wt.%, 1.50 wt.% ≤ dCo ≤ 5.00 wt.%, 0.50 wt.% ≤ dMn ≤ 4.75 wt.%.

13. Alloy according to claim 1, characterized in that 48.00 wt.% ≤ a Ni + a Cu ≤ 51.00 wt%, 42.00 wt% ≤ b Nb + b Ta≤ 50.00 wt.%, 0 wt.% < i ≤ 1.40 wt.%, preferably 0.85 wt.% ≤ i ≤ 0.95 wt.%, 0.50 wt.% ≤ e V + e Mo ≤ 8.50 wt.%, c Zr + c Hf + c Ti = d Fe + d Cr + d Co + d Mn = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = a Cu = b Ta = 0 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, preferably 0.50 wt.% ≤ e V ≤ 4.50% by weight, 1.25% by weight ≤ e Mo ≤ 8.10 wt.%.

14. Alloy according to claim 1 or 2, characterized in that, Page 4 / 6 that 48.00 wt.% ≤ a Ni + a Cu ≤ 51.00 wt%, 42.00 wt% ≤ b Nb + b Ta ≤ 50.00 wt.%, 0.10 wt.% < i ≤ 1.40 wt.%, preferably 0.85 wt.% ≤ i ≤ 0.95 wt.%, 0.50 wt.% ≤ eV + eMo ≤ 5.00 wt.%, cZr + cHf + cTi = dFe + dCr + dCo + dMn = fSn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = g B + g C = a Cu = b Ta = 0 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, preferably 0.50 wt.% ≤ e V ≤ 4.50% by weight, 1.25% by weight ≤ e Mo ≤ 4.50 wt.%.

15. Alloy according to claim 1 or 2, characterized in that 46.00 wt.% ≤ a Ni + a Cu ≤ 49.00 wt%, 41.00 wt% ≤ b Nb + b Ta ≤ 51.00 wt.%, 0.10 wt.% < i ≤ 1.40 wt.%, preferably 0.84 wt.% ≤ i ≤ 0.89 wt.%, 0.35 wt.% ≤ f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb ≤ 10.00 wt.%, c Zr + c Hf + c Ti = dFe + dCr + dCo + dMn = eV + eMo = gB + gC = aCu = bTa = 0 wt.%, 0 wt.% ≤ hO + hH + h N ≤ 0.10 wt.%, preferably 3.25 wt.% ≤ f Sn≤ 10.00% by weight, 1.25% by weight ≤ f Ag ≤ 5.00% by weight, 0.75% by weight ≤ f Zn ≤ 3.00% by weight, 0.25% by weight ≤ f Al ≤ 1.25% by weight, 0.25% by weight ≤ f Si ≤ 1.00% by weight, 0.75% by weight ≤ f Ge ≤ 2.75% by weight, 1.50% by weight ≤ f Sb ≤ 5.25 wt.%.

16. Alloy according to claim 1 or 2, characterized in that 48.00 wt.% ≤ a Ni + a Cu ≤ 49.00 wt%, 50.00 wt% ≤ b Nb + b Ta ≤ 51, wt.%, 0.10 wt.% < i ≤ 1.40 wt.%, preferably 0.75 wt.% ≤ i ≤ 0.90 wt.%, preferably i = 0.87 wt.%, 0.10 wt.% ≤ gB + gC ≤ 0.60 wt.%, cZr + cHf + cTi = d Fe + d Cr + d Co + d Mn = e V + e Mo = f Sn + f Ag + f Zn + f Al + f Si + f Ge + f Sb = a Cu = b Ta = 0 wt%, 0 wt% ≤ h O + h H + h N ≤ 0.10 wt.%, preferably 0.10 wt.% ≤ g B≤ 0.50 wt%, 0.10 wt% ≤ g C ≤ 0.55 wt.%.

17. Alloy according to one of claims 1 to 16, characterized in that a critical casting thickness D c between 0.5 mm and 7.0 mm.

18. Alloy according to one of claims 1 to 17, characterized in that the alloy has a Vickers hardness (HV5) between 840 and 1050, determined according to ISO 6507. Page 5 / 6 19. An alloy according to any one of claims 1 to 18, characterized in that the alloy has a fracture strength between 2.5 GPa and 5.5 GPa, the fracture strength being determined in a 3-point bending test.

20. A molded article made from an alloy according to any one of claims 1 to 19, preferably by suction or pressure casting. Page 6 / 6

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