DE102016008074A1 - Solid glass-forming white gold alloy - Google Patents

Abstract

A white gold alloy of the composition (Au1-a-bAga (Pd1-cPtc) b) 100-xy (CU1-deLdMe) x (Si1-fGef) y was prepared wherein: L is In, Ga or Sn or Ld is L1 d1L2 d2 or L1 d1L2 d2L3 d3, wherein L1, L2 and L3 are selected from the elements In, Ga or Sn, and M is one or more elements of the elements Ni, Co and Fe; x and y are at%, where x = 10-30 at%, y = 10-16.3 at%, where (100-xy) and x and y may contain unavoidable trace impurities, a, b, c, d, e and f is a fraction of 1, where a = 0.02-0.20, b = 0-0.1, c = 0-1, d = 0.02-0.40, d1 = 0-0.4 ; d2 = 0 to 0.4; d3 = 0 to 0.4, where d1 + d2 + d3 = d, e = 0-0.12 (total fraction of elements Ni, Co and Fe) and f = 0-0.40. The white gold alloy is solid glass forming in a wide range and suitable for jewelry applications.

Description

Field of the invention

The invention relates to a white gold alloy, which can form solid glasses in many areas.

Background of the invention

Metallic solid glasses are alloys that solidify at sufficiently high cooling rates to form amorphous solids. Due to their amorphous structure, metallic solid glasses have properties that make them far superior to conventional metal alloys.

The lack of a volume jump by crystallization of the sample can be made of solid glass forming alloys near net shape castings, which require a minimum of post-processing. Near-eutectic alloys exhibit excellent casting properties due to their low liquidus temperature. Furthermore, amorphous semifinished product (z, B. granules) can be heated out of the glass into the area of the supercooled melt and reshaped.

Metallic solid glasses can also have much higher hardness than crystalline alloys.

However, the composition of metallic solid glass can not be changed arbitrarily, since a glass formation is usually possible only in very limited concentration ranges.

Among other things, hard gold alloys are very desirable for the production of jewelry. Crystalline gold alloys only reach values of 100 to 250 HV, even with enormous cold forming. An exception is red gold, which can reach hardnesses above 300 HV.

State of the art

From the US 8 501 087 B2 is a gold alloy having the composition: (Au _1-x (Ag _1-y (Pd, Pt) _y ) _x ) _a (Cu _1-z (NI, CO, Fe, Cr, Mn) _z ) _b ((Si _{1 -V} P _v ) _1-w (Ge, Al, Y, Be) _w ) _c where a, b, c are at% (atomic percent), x, y, z, v and w are fractions of 1, a is in the range of about 25 to about 75 at%, b is in the range of about 10 about 50 at%, c is in the range of about 12 to about 30 at%, and for fractions x, y, z, v and w The following restrictions apply: x is 0 to 0.5; y is 0 to 1; z is 0 to 0.5; v is 0 to 0.5 and w is 0 to 1. Some of these alloys form solid glasses, including the alloy Au ₄₉ Ag _5.5 Pd _2.3 Cu _26.9 Si _16.3 [Au-BMG1], which is a white-gold Owns color and is classified in the polished state as "Premium White". The glass transition temperature (Tg) is 128 ° C.

However, this alloy shows a strong discoloration (down to the off-white range [1]) [2, 3]. This process takes place under different conditions, but is particularly pronounced in experiments with artificial saliva or artificial sweat. The strong color change, also referred to as "tarnish", is observed among other things also at room temperature or slightly elevated temperatures such as body temperature. Investigations by the inventors [1] have shown that the combination of the three main constituents (gold, copper, silicon) is responsible for the start-up process [2, 3]. The corrosion mechanism is characterized by the formation of amorphous silica branches growing in the base material and copper oxide layers on the surface. The rapid formation of silica at such low temperatures is very unusual, but has also been found in crystalline systems in the combination of silicon and copper [5, 6]. Au-Cu-Si based alloys show low nucleation temperatures along the Au-Cu axis at silicon concentrations of about 15-20 at% and solidify at sufficiently high cooling rates to form a glass. Replacing Cu with Au results in the glass transition temperature dropping far below 100 ° C, [7] making the alloys less suitable for jewelry applications. A low copper content does not necessarily lead to a higher corrosion resistance [1].

Another massive glass-forming gold alloy with the composition Au ₅₀ Sn ₆ Cu ₂₆ Si ₁₈ is made Wang and T. Chin, "Tin - Modified Gold-Based Bulk Metallic Glasses", Gold Bull. (2012) 45: 3-8 , [8] known. This alloy has a very low Tg of 82 ° C, making it less suitable for jewelry applications. On the other hand, obviously only a casting thickness of 1 mm could be achieved for the alloy,

When cast, these alloys can reach a hardness of up to 360 HV. The thermoplastic molding process of these alloys may take place in a temperature range of about 100 to about 160 ° C, depending on the alloy composition.

The aim of the invention was to provide a suitable for jewelry applications gold alloy, which can form solid glass in a wide range and less color change or corrosion z. B. when wearing a jewelry made from it.

Summary of the invention

The invention relates to an alloy of the composition. The invention relates to an alloy of the composition:
(Au _1-ab Ag _a (Pd _{1 -c} Pt _c ) _b ) _100-xy (Cu _1-de L _d M _e ) _x (Si _1-f Ge _f ) _y
wherein:
L stands for In, Ga or Sn or
L _{d is} L ¹ _d1 L ² _d2 or L ¹ _d1 L ² _d2 L ³ _d3 , wherein L ¹ , L ² and L ^{3 are selected} from the elements In, Ga or Sn, and M is one or more of the elements Elements Ni, Co and Fe are;
x and y are at%, where
x = 10-30 at%,
y = 10-16.3 at%,
where (100-xy) and x and y may contain unavoidable trace impurities,
a, b, c, d, e and f are a fraction of 1, where
a = 0.02-0.20,
b = 0-0.1,
c = 0-1,
d = 0.02-0.40,
d1 = 0 to 0.4;
d2 = 0 to 0.4;
d3 = 0 to 0.4, where
d1 + d2 + d3 = d,
e = 0-0.12 (total fraction of elements Ni, Co and Fe) and
f = 0-0.40,
except the following alloys:
Au ₄₉ Ag _5.5 Pd _2.3 Cu _25.9 Sn ₁ Si _16.3 ,
Au ₄₉ Ag _5.5 Pd _2.3 Cu _25.9 Ga ₁ Si _16.3 ,
Au _65.2 Ag ₅ Cu ₅ Ga _9.3 Si _15.5 ,
Au _52.11 Ag _7.52 Cu _15.57 Ga _9.3 Si _15.5 .

Another object of the invention is the production of this alloy and its use in the jewelry sector.

Brief description of the figures

The 1 - 3 show thermal DSC analyzes of three different alloy compositions according to the invention. The glass transition, the area of the supercooled melt and the crystallization event are clearly visible up to a thickness of 3 mm.

Fig. 1: Alloy composition (at%):

• Au51,59Ag5,79Pd2,42Cu20,175Ga6,725Si13,3 ("NGL6")

Fig. 2: Alloy composition (at%):

• Au52.59Ag5.79Pd2.42Cu18.675Ga8.22Si12.3 ("NGL8")

Fig. 3: Alloy composition (at%):

• Au48.5Ag9.88Pd2.42Cu18.675Ga8.22Si12.30 ("NGL8_Ag_Max")

Detailed description

It has surprisingly been found that white gold alloys having the composition (Au _1-from Ag _a (Pd _1-c Pt _{c)) 100-xy} (Cu _1-de L _d M _{e) x} (Si _1-f Ge _{f) y,} wherein L is In, Ga or Sn or L _{d is} L ¹ _d1 L ² _d2 or L ¹ _d1 L ² _d2 L ³ _d3 , wherein L ¹ , L ² and L ^{3 are selected} from the elements In, Ga or Sn , M is one or more elements of the elements Ni, Co and Fe and a, b, c, d, e, f, x and y are as defined above, forming solid glasses in a wide compositional range.

It was surprisingly found that, for. B. in comparison to the known solid glass-forming alloy Au ₄₉ Ag _5.5 Pd _2.3 Cu _26.9 Si _16.3 , while reducing the silicon content of copper by in particular In, Ga and / or Sn can be substiutiert without the Massive glass formation is lost, reducing the susceptibility to corrosion.

In alloys preferred for jewelry applications, e = 0.

Further, a = 0.075-0.12, more preferably a = 0.085-0.12.

Further, in preferred alloy compositions, depending on the application, y, y, a, b, d, d1, d2, d3, e and f are as follows:

Alloy Composition 1A:

• x = 10-30 at%,
• y = 10-16.3 at%,
• a = 0.05-0.15,
• b = 0.02-0.08,
• c = 0-0.5
• d = 0.075-0.35,
• d1 = 0 to 0.35;
• d2 = 0 to 0.35;
• d3 = 0 to 0.35; and
• d1 + d2 + d3 = d,
• e = 0,
• f = 0-0.20.

Alloy Composition 1B:

• x = 15-27 at%,
• y = 12-16.3 at%,
• a = 0.05-0.15,
• b = 0.02-0.08,
• c = 0-0.5,
• d = 0.075-0.35,
• d1 = 0 to 0.35;
• d2 = 0 to 0.35;
• d3 = 0 to 0.30; and
• d1 + d2 + d3 = d.
• e = 0,
• f = 0-0.20.

Alloy Composition 1C:

• x = 15-27 at%,
• y = 12-16.3 at%,
• a = 0.075-0.12,
• b = 0.03-0.065,
• c = 0
• d = 0.1-0.30,
• d1 = 0 to 0.30;
• d2 = 0 to 0.30;
• d3 = 0 to 0.30; and
• d1 + d2 + d3 = d,
• e = 0,
• f = 0.

Alloy composition 1D:

• x = 20-27 at%,
• y = 12-16 at%,
• a = 0.075-0.12,
• b = 0.03-0.065,
• c = 0
• d = 0.1-0.30,
• d1 = 0 to 0.30;
• d2 = 0 to 0.30;
• d3 = 0 to 0.30; and
• d1 + d2 + d3 = d,
• e = 0,
• f = 0.

Alloy composition 1E:

• x = 20-27 at%,
• y = 12-16 at%,
• a = 0.085-0.12,
• b = 0.036-0.05,
• c = 0,
• d = 0.2-0.28,
• d1 = 0 to 0.28;
• d2 = 0 to 0.28;
• d3 = 0 to 0.28; and
• d1 + d2 + d3 = d,
• e = 0,
• f = 0.

Alloy composition 1F:

• x = 24-27 at%,
• y = 12-14 at%,
• a = 0.085-0.12,
• b = 0.036-0.05,
• c = 0,
• d = 0.2-0.28,
• d1 = 0 to 0.28;
• d2 = 0 to 0.28;
• d3 = 0 to 0.28; and
• d1 + d2 + d3 = d
• e = 0,
• f = 0.

Alloy composition 1G

• x = 24-27 at%,
• y = 12-14 at%,
• a = 0.095-0.1,
• b = 0.036-0.05,
• c = 0
• d = 0.24-0.26,
• d1 = 0 to 0.26;
• d2 = 0 to 0.26;
• d3 = 0 to 0.26; and
• d1 + d2 + d3 = d
• e = 0,
• f = 0.

Alloy Composition 2A

• x = 20-27 at%,
• y = 10-14.3 at%,
• a = 0.05-0.15,
• b = 0.02-0.08,
• c = 0-0.5,
• d = 0.25-0.35,
• d1 = 0 to 0.35;
• d2 = 0 to 0.35;
• d3 = 0 to 0.30; and
• d1 + d2 + d3 = d.
• e = 0,
• f = 0-0.20.

Alloy Composition 2B:

• x = 25-27 at%,
• y = 10-13.3 at%,
• a = 0.05-0.15,
• b = 0.02-0.08,
• c = 0,
• d = 0.3-0.35,
• d1 = 0 to 0.35;
• d2 = 0 to 0.35;
• d3 = 0 to 0.30; and
• d1 + d2 + d3 = d.
• e = 0,
• f = 0.

The preparation of the alloys can be accomplished as follows.

The purity of the starting element materials employed is not particularly critical, but more than 99%, preferably more than 99.9%, more preferably at least 99.99%, purity is often desirable. Also, the particular shape of the starting material materials (eg, granules, platelets, flakes) is not critical.

The starting material materials are weighed according to the desired stoichiometry with a precision balance. Subsequently, the output elements in a suitable device, for. As a modified (water cooling, improved seals) Kippgussanlage (eg Indutherm MC15), in a suitable crucible, z. As an alumina crucible with or without Zirkonoxidbeschichtung arranged. For example, the following order of elements in the crucible can be maintained (from bottom to top): Pd / Pt-Ag-Au-Cu / Ni / Co / Fe-Ga / Sn / In-Si / Ge, since this results in the formation of palladium - and / or platinum silicides is unlikely. However, a different order of the elements in the crucible can also lead to the desired result. The elements are inductively melted and homogenized. The melt is slowly heated to a temperature (effluent temperature) generally well above the liquidus temperature, typically about 400-450 ° C above, to ensure melt homogeneity, but longer residence times may also result in lower effluent temperatures. The temperature is constantly controlled by a pyrometer. Once the desired effluent temperature has been reached, the melt is poured into a suitable mold, e.g. As a water-cooled copper mold poured. The process preferably takes place under inert gas (Ar or N ₂ ). The casting can also be carried out in a vacuum. Already alloyed and remelted material can be cast at lower temperatures.

Alternatively, the individual elements can also be melted and homogenized in an electric arc furnace. The alloys can also be centrifugally cast in the uncooled copper molds can be used. Furthermore, the use of pressure-assisted casting process for the production of amorphous castings is possible (die-casting, suction casting method).

In this way, z. B. jewelry directly pour.

It is also possible to produce amorphous granules. These can then be used as semi-finished products for thermoplastic molding (TPF) or 3D printing processes. For example, rods of the new alloys with a diameter of 2-3 mm were produced and thermoformed. It is obvious that jewelry can also be formed in this way.

Other applications of the new alloys, such as in dental prostheses, nanoimprinting and micro-electromechanical systems (MEMS), are of course also possible.

Examples

Example 1: Preparation Example for the alloy Au _51.59 Ag _{5.79 2:42} Pd Cu Ga _{20.175 6.725} Si _13.3

The pure elements (purity: Au (granules 1-5 mm), Ag (platelets), Pd (platelets): highest commercial purity; In: 99.9975% (granules 1-5 mm), Ga: 99.9999% (granules 1-5 mm), Sn: 99.995% (granules 1-5 mm), Cu: 99.99% (granules 1-5 mm), Si: 99.9995% (flakes)) were weighed with a fine balance. For the preparation of the alloy Au 10 g _51.59 Ag _{5.79 2:42} Pd Cu Ga _{20.175 6.725 13.3} Si (at%) of 7.7168 g Au, Ag 0.4743 g, 0.1956 g Pd, Cu 0.9736 g, 0, Weighed in 3561 g of Ga and 0.2837 g of Si. Subsequently, the elements were positioned in an alumina crucible in a modified (water cooled, improved gaskets) tilt casting facility (Indutherm MC15). The following order of the elements in the crucible was observed: (from bottom to top): Pd-Ag-Au-Cu-Ga-Si.

The elements were inductively melted and homogenized. The melt was heated slowly to a temperature of 1100 ° C-1200 ° C, the temperature was constantly monitored by a pyrometer. When the desired effluent temperature of 1100 ° C-1200 ° C was reached, the melt was poured into the water-cooled copper mold. The process took place under protective gas (Ar).

The prepared sample is a rod with a diameter of 3 mm. The sample has a premium white color (according to classification of white gold alloys by the Yellowness Index (YI D1925)). The glass transition temperature is 103 ° C at a heating rate of 20 ° C / min.

The crystallization starts at 155 ° C. The solidus temperature is 340 ° C, the liquidus temperature 408 ° C.

Example 2: Prepared massive glass-forming alloys

The following alloys were prepared in a similar manner to Example 1: TABLE 1 Composition: Critical thickness (d _c ) [mm] Glass transition temperature (Tg) [° C] Au49Ag5,5Pd2,3Cu23,54Ga3,36Si16,3 d _c > 3 Au49Ag5,5Pd2,3Cu20,18Ga6,72Si16,3 1> d ≥ 0.25 Au50.5Ag5.5Pd2.3Cu23.54Ga3.36Si14.8 (NGL5.1) d _c ≥ 3 Au50,29Ag5,65Pd2,36Cu23,54Ga3,36Si14,8 (NGL5) d _c ≥ 3 Au51,59Ag5,79Pd2,42Cu20,175Ga6,725Si13,3 (NGL6) d _c ≥ 3 101 Au52Ag5.5Pd2.3Cu20.175Ga6.725Si13.3 (NGL6.1) d _c ~ 3 Au54,1Ag6,05Pd2,15Cu16,81Ga10,09Si10,8 _dc = 1 Au51,59Ag5,79Pd2,42Cu18,175Ga8,725Si13,3 d _c ≥ 3 Au51,59Ag5,79Pd2,42Cu19,675Ga8,725Si13,3 3> d _c ≥ 1 Au51,59Ag5,79Pd2,42Cu19,675Ga7,225Si13,3 d> 1 Au52.59Ag5.79Pd2.42Cu18.675Ga8.225Si12.3 (NGL8) d _c ~ 3 98 NGL6 Variations: Au52,5Ag4,88Pd2,42Cu20,175Ga6,725Si13,3 > 1 Au52Ag5,38Pd2,42Cu20,175Ga6,725Si13,3 > 1 Au51,59Ag5,79Pd2,42Cu20,175Ga6,725Si13,3 (NGL6) > 1 Au51Ag6,38Pd2,42Cu20,175Ga6,725Si13,3 > 1 Au50,5Ag6,88Pd2,42Cu20,175Ga6,725Si13,3 > 1 Au49,5Ag7,88Pd2,42Cu20,175Ga6,725Si13,3 > 1 Au51,99Ag5,79Pd2,02Cu20,175Ga6,725Si13,3 > 1 101 Au51,79Ag5,79Pd2,22Cu20,175Ga6,725Si13,3 > 1 Au51,39Ag5,79Pd2,62Cu20,175Ga6,725Si13,3 > 1 Au51,19Ag5,79Pd2,82Cu20,175Ga6,725Si13,3 > 1 NGL8 Variations: Au53,5Ag4,88Pd2,42Cu18,675Ga8,225Si12,30 > 1 Au53Ag5,38Pd2,42Cu18,675Ga8,225Si12,30 > 1 Au52.59Ag5.79Pd2.42Cu18.675Ga8.22Si12.3 (NGL8) > 1 98 Au52Ag6,38Pd2,42Cu18,675Ga8,225Si12,30 > 1 Au51,5Ag6,88Pd2,42Cu18,675Ga8,225Si12,30 > 1 Au50,5Ag7,88Pd2,42Cu18,675Ga8,225Si12,30 > 1 Au48,5Ag9,88Pd2,42Cu18,675Ga8,225Si12,30 > 1 Au52,99Ag5,79Pd2,02C118,675Ga8,225Si12,30 > 1 Au52,79Ag5,79Pd2,22Cu18,675Ga8,225Si12,30 > 1 Au52,39Ag5,79Pd2,62Cu18,675Ga8,225Si12,30 > 1 Au52,19Ag5,79Pd2,82Cu18,675Ga8,225Si12,30 > 1 36Si16,3; Au49Ag5,5Pd2,3Cu23,54Sn3 3d _c Au49Ag5,5Pd2,3Cu20,175Sn6,725Si16,3 ~ 1 Au50,29Ag5,65Pd2,36Cu23,54Sn3,36Si14,8 3 ≤ d _c Au51,59Ag5,79Pd2,42Cu20,175Sn6,725Si13,3 3 ≤ d _c Au49Ag5,5Pd2,3Cu23,541n3,36Si16,3 3 ≤ d _c Au49Ag5,5Pd2,3Cu20,1751n6,725Si16,3 1 ≤ d _c <3 Au51,59Ag5,79Pd2,42Cu20,1751n6,725Si13,3 Au51,59Ag5,79Pd2,42Cu20,181n3,36Sn3,36Si13,3 Au51,59Ag5,79Pd2,42Cu20,181n3,366a3,36Si13,3 Au51,59Ag5,79Pd2,42Cu20,18Ga3,36Sn3,36Si13,3

The critical thickness of the samples (the thickness to which the sample remains amorphous) was determined by making samples of different diameter. The completely amorphous character of the samples was confirmed by X-ray diffractometry (Cu Kalpha, 20 ° <2θ <80 °). In addition, the crystallization enthalpy of the respective X-ray amorphous 1 mm sample was determined in calorimetric measurements (Perkin Elmer DSC8500). By comparing the crystallization enthalpies, the fully amorphous character of thicker samples can be confirmed.

bibliography

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• [3] Eisenbart, M ,, Klotz, U, E., Busch, R ,, & Gallino, I. On the abnormal room tennature, tarnishing of an 18k gold bulk metallic glass altoy. (2014) Journal of Alloys and Compounds, 615, S118-S122 ,
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QUOTES INCLUDE IN THE DESCRIPTION

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Cited patent literature

• US 8501087 B2 [0007]

Cited non-patent literature

• Wang and T. Chin, "Tin - Modified Gold-Based Bulk Metallic Glasses", Gold Bull. (2012) 45: 3-8 [0009]

Claims (10)

White gold alloy of composition: (Au _1-ab Ag _a (Pd _{1 -c} Pt _c ) _b ) _100-xy (Cu _1-de L _d M _e ) _x (Si _1-f Ge _f ) _y where: L is In, Ga or Sn or L _{d is} L ¹ _d1 L ² _d2 or L ¹ _d1 L ² _d2 L ³ _d3 , wherein L ¹ , L ² and L ^{3 are selected} from the elements In, Ga or Sn, and M is a or more elements of the elements Ni, Co and Fe; x and y are at%, where x = 10-30 at%, y = 10-16.3 at%, where (100-xy) and x and y may contain unavoidable trace impurities, a, b, c, d, e and f is a fraction of 1, where a = 0.02-0.20, b = 0-0.1, c = 0-1, d = 0.02-0.40, d1 = 0-0.4 ; d2 = 0 to 0.4; d3 = 0 to 0.4, where d1 + d2 + d3 = d, e = 0-0.12 (total fraction of elements Ni, Co and Fe) and f = 0-0.40 except for the following alloys Au ₄₉ Ag _5.5 Pd _2.3 Cu _25.9 Sn ₁ Si _16.3 , Au ₄₉ Ag _5.5 Pd _2.3 Cu _25.9 Ga ₁ Si _16.3 , Au _65.2 Ag ₅ Cu ₅ Ga _9.3 Si _15.5 , Au _52.11 Ag _7.52 Cu _15.57 Ga _9.3 Si _15.5 . White gold alloy according to claim 1, characterized in that e = 0. White gold alloy according to claim 1 or 2, characterized in that a = 0.075-0.12, preferably a = 0.085-0.12. White gold alloy according to claim 1 or 2, characterized in that x = 10-30 at%, y = 10-16.3 at%, a = 0.05-0.15, b = 0.02-0.08, c = 0-0.5 d = 0.075-0.35, d1 = 0 to 0.35; d2 = 0 to 0.35; d3 = 0 to 0.35; and d1 + d2 + d3 = d, e = 0, f = 0-0.20. White gold alloy according to one of claims 1 to 4, characterized in that x = 15-27 at%, y = 12-16.3 at%, a = 0.075-0.12, b = 0.03-0.065, c = 0 d = 0.1-0.30, d1 = 0 to 0.30; d2 = 0 to 0.30; d3 = 0 to 0.30; and d1 + d2 + d3 = d, e = 0, f = 0. White gold alloy according to one of claims 1 to 5, characterized in that x = 20-27 at%, y = 12-16 at%, a = 0.085-0.12, b = 0.036-0.05, c = 0, d = 0.2-0.28, d1 = 0 to 0.28; d2 = 0 to 0.28; d3 = 0 to 0.28; and d1 + d2 + d3 = d, e = 0, f = 0. White gold alloy according to one of claims 1 to 6, characterized in that x = 24-27 at%, y = 12-14 at%, a = 0.095-0.1, b = 0.036-0.05, c = 0 d = 0.24-0.26, d1 = 0 to 0.26; d2 = 0 to 0.26; d3 = 0 to 0.26; and d1 + d2 + d3 = de = 0, f = 0. White gold alloy according to claim 1 or 2, characterized in that x = 25-27 at%, y = 10-13.3 at%, a = 0.05-0.15, b = 0.02-0.08, c = 0, d = 0.3-0.35, d1 = 0 to 0.35; d2 = 0 to 0.35; d3 = 0 to 0.30; and d1 + d2 + d3 = d. e = 0, f = 0. A method for producing a white gold alloy according to any one of claims 1 to 8, wherein the starting material materials are weighed according to desired stoichiometry and placed in a suitable crucible, then inductively melted and homogenized, the melt then slowly heated to a desired effluent temperature above the liquidus In order to ensure the homogeneity of the melt and the melt is then poured into a suitable mold, preferably the following order of the elements in the crucible from bottom to top are met: Pd / Pt-Ag-Au-Cu / Ni / Co / Fe -ga / Sn / In-Si / Ge. Use of a white gold alloy according to any one of claims 1 to 8 in the manufacture of jewelry.

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