EP3695920A1 - Robust ingot for the production of components made of metallic solid glasses - Google Patents
Robust ingot for the production of components made of metallic solid glasses Download PDFInfo
- Publication number
- EP3695920A1 EP3695920A1 EP19156906.0A EP19156906A EP3695920A1 EP 3695920 A1 EP3695920 A1 EP 3695920A1 EP 19156906 A EP19156906 A EP 19156906A EP 3695920 A1 EP3695920 A1 EP 3695920A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- ingot
- melt
- alloy
- glass
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 239000007787 solid Substances 0.000 title claims abstract description 61
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 239000011521 glass Substances 0.000 title claims description 25
- 238000005266 casting Methods 0.000 claims abstract description 89
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 81
- 239000000956 alloy Substances 0.000 claims abstract description 81
- 238000007496 glass forming Methods 0.000 claims abstract description 42
- 239000000155 melt Substances 0.000 claims abstract description 40
- 238000001816 cooling Methods 0.000 claims abstract description 20
- 230000009477 glass transition Effects 0.000 claims abstract description 16
- 238000000034 method Methods 0.000 claims description 32
- 239000000463 material Substances 0.000 claims description 17
- 238000002844 melting Methods 0.000 claims description 15
- 230000008018 melting Effects 0.000 claims description 15
- 230000015572 biosynthetic process Effects 0.000 claims description 6
- 229910052582 BN Inorganic materials 0.000 claims description 2
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 2
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 claims description 2
- 230000014759 maintenance of location Effects 0.000 claims 1
- 238000005259 measurement Methods 0.000 description 26
- 239000000523 sample Substances 0.000 description 25
- 239000010949 copper Substances 0.000 description 17
- 238000000113 differential scanning calorimetry Methods 0.000 description 15
- 238000010438 heat treatment Methods 0.000 description 15
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 14
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 13
- 229910052802 copper Inorganic materials 0.000 description 13
- 238000002425 crystallisation Methods 0.000 description 10
- 230000008025 crystallization Effects 0.000 description 10
- 239000005300 metallic glass Substances 0.000 description 10
- 239000010936 titanium Substances 0.000 description 9
- 229910052723 transition metal Inorganic materials 0.000 description 9
- 229910052751 metal Inorganic materials 0.000 description 8
- 239000002184 metal Substances 0.000 description 8
- 150000003624 transition metals Chemical class 0.000 description 8
- 229910000831 Steel Inorganic materials 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 7
- 229910052796 boron Inorganic materials 0.000 description 7
- 239000010959 steel Substances 0.000 description 7
- KDLHZDBZIXYQEI-UHFFFAOYSA-N Palladium Chemical compound [Pd] KDLHZDBZIXYQEI-UHFFFAOYSA-N 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 239000011248 coating agent Substances 0.000 description 6
- 238000000576 coating method Methods 0.000 description 6
- 238000001746 injection moulding Methods 0.000 description 6
- 150000002739 metals Chemical class 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 229910052759 nickel Inorganic materials 0.000 description 5
- 239000010955 niobium Substances 0.000 description 5
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 5
- 230000007704 transition Effects 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 229910019086 Mg-Cu Inorganic materials 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 4
- 229910052733 gallium Inorganic materials 0.000 description 4
- 230000001939 inductive effect Effects 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 4
- 229910052710 silicon Inorganic materials 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910052684 Cerium Inorganic materials 0.000 description 3
- 229910006291 Si—Nb Inorganic materials 0.000 description 3
- 229910052771 Terbium Inorganic materials 0.000 description 3
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 3
- 239000004411 aluminium Substances 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 238000010891 electric arc Methods 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 229910052746 lanthanum Inorganic materials 0.000 description 3
- 238000000691 measurement method Methods 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- QEFYFXOXNSNQGX-UHFFFAOYSA-N neodymium atom Chemical compound [Nd] QEFYFXOXNSNQGX-UHFFFAOYSA-N 0.000 description 3
- 229910052763 palladium Inorganic materials 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 150000002910 rare earth metals Chemical class 0.000 description 3
- 229910052715 tantalum Inorganic materials 0.000 description 3
- GZCRRIHWUXGPOV-UHFFFAOYSA-N terbium atom Chemical compound [Tb] GZCRRIHWUXGPOV-UHFFFAOYSA-N 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- 239000011701 zinc Substances 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 229910017944 Ag—Cu Inorganic materials 0.000 description 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- 229910017755 Cu-Sn Inorganic materials 0.000 description 2
- 229910002482 Cu–Ni Inorganic materials 0.000 description 2
- 229910017870 Cu—Ni—Al Inorganic materials 0.000 description 2
- 229910017888 Cu—P Inorganic materials 0.000 description 2
- 229910017927 Cu—Sn Inorganic materials 0.000 description 2
- 229910052688 Gadolinium Inorganic materials 0.000 description 2
- GYHNNYVSQQEPJS-UHFFFAOYSA-N Gallium Chemical compound [Ga] GYHNNYVSQQEPJS-UHFFFAOYSA-N 0.000 description 2
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- 229910001257 Nb alloy Inorganic materials 0.000 description 2
- 229910052779 Neodymium Inorganic materials 0.000 description 2
- 229910017709 Ni Co Inorganic materials 0.000 description 2
- 229910003267 Ni-Co Inorganic materials 0.000 description 2
- 229910018104 Ni-P Inorganic materials 0.000 description 2
- 229910003262 Ni‐Co Inorganic materials 0.000 description 2
- 229910018536 Ni—P Inorganic materials 0.000 description 2
- 229910021074 Pd—Si Inorganic materials 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 229910008310 Si—Ge Inorganic materials 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 229910004337 Ti-Ni Inorganic materials 0.000 description 2
- 229910011209 Ti—Ni Inorganic materials 0.000 description 2
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 2
- 229910003126 Zr–Ni Inorganic materials 0.000 description 2
- 239000011575 calcium Substances 0.000 description 2
- 229910052791 calcium Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 229910003460 diamond Inorganic materials 0.000 description 2
- 239000010432 diamond Substances 0.000 description 2
- UIWYJDYFSGRHKR-UHFFFAOYSA-N gadolinium atom Chemical compound [Gd] UIWYJDYFSGRHKR-UHFFFAOYSA-N 0.000 description 2
- 229910052732 germanium Inorganic materials 0.000 description 2
- GNPVGFCGXDBREM-UHFFFAOYSA-N germanium atom Chemical compound [Ge] GNPVGFCGXDBREM-UHFFFAOYSA-N 0.000 description 2
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 2
- 229910052737 gold Inorganic materials 0.000 description 2
- 239000010931 gold Substances 0.000 description 2
- 229910052735 hafnium Inorganic materials 0.000 description 2
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 2
- KHYBPSFKEHXSLX-UHFFFAOYSA-N iminotitanium Chemical compound [Ti]=N KHYBPSFKEHXSLX-UHFFFAOYSA-N 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 2
- 239000011777 magnesium Substances 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 229910001092 metal group alloy Inorganic materials 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 229910052755 nonmetal Inorganic materials 0.000 description 2
- 150000002843 nonmetals Chemical class 0.000 description 2
- 229910052697 platinum Inorganic materials 0.000 description 2
- 229910052706 scandium Inorganic materials 0.000 description 2
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 2
- 229910052718 tin Inorganic materials 0.000 description 2
- 229910052727 yttrium Inorganic materials 0.000 description 2
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- -1 Co-(Al Inorganic materials 0.000 description 1
- 238000005169 Debye-Scherrer Methods 0.000 description 1
- 241001523162 Helle Species 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- AFCARXCZXQIEQB-UHFFFAOYSA-N N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CCNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 AFCARXCZXQIEQB-UHFFFAOYSA-N 0.000 description 1
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 230000002730 additional effect Effects 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 238000009529 body temperature measurement Methods 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 239000003086 colorant Substances 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000001382 dynamic differential scanning calorimetry Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000011888 foil Substances 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 238000002074 melt spinning Methods 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 238000000399 optical microscopy Methods 0.000 description 1
- SIWVEOZUMHYXCS-UHFFFAOYSA-N oxo(oxoyttriooxy)yttrium Chemical compound O=[Y]O[Y]=O SIWVEOZUMHYXCS-UHFFFAOYSA-N 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000010970 precious metal Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000003678 scratch resistant effect Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229920001169 thermoplastic Polymers 0.000 description 1
- 239000004416 thermosoftening plastic Substances 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 229910052845 zircon Inorganic materials 0.000 description 1
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D25/00—Special casting characterised by the nature of the product
- B22D25/06—Special casting characterised by the nature of the product by its physical properties
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22C—FOUNDRY MOULDING
- B22C3/00—Selection of compositions for coating the surfaces of moulds, cores, or patterns
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
- B22D27/04—Influencing the temperature of the metal, e.g. by heating or cooling the mould
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/023—Alloys based on nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/11—Making amorphous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C16/00—Alloys based on zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/02—Amorphous alloys with iron as the major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/04—Amorphous alloys with nickel or cobalt as the major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/10—Amorphous alloys with molybdenum, tungsten, niobium, tantalum, titanium, or zirconium or Hf as the major constituent
Definitions
- the invention relates to a method for the production of mechanically and thermally stable ingots (also called preforms) from alloys which can form a metallic solid glass.
- the invention further relates to an ingot of a solid glass-forming alloy which is produced using the method according to the invention and the use of this ingot in a casting process.
- Metallic glasses have been the subject of extensive research since their discovery at the California Institute of Technology about 50 years ago. Over the years it has been possible to continuously improve the processability and properties of this class of materials. While the first metallic glasses were still simple, binary alloys (made up of two components), the production of which required cooling rates in the range of 10 6 Kelvin per second (K / s), newer, more complex alloys can already be produced at significantly lower cooling rates in the range of a few K. / s in the glass state. This has a significant impact on process management and the components that can be implemented. The cooling rate at which the melt does not crystallize and the melt solidifies as glass is referred to as the critical cooling rate.
- Today's glass-forming metallic alloys can be converted into the glass state by pouring a melt into cooled copper molds.
- the realizable component thicknesses are alloy-specific in the range of a few millimeters to centimeters.
- Such alloys are called solid metallic glasses (English: Bulk Metallic Glasses, BMG).
- BMG Bulk Metallic Glasses
- a metallic solid glass is to be understood as a material with a critical casting thickness of at least one millimeter.
- a large number of such alloy systems are known today. They are usually subdivided on the basis of their composition, with the alloy element with the highest weight percentage being called the base element.
- the existing systems include precious metal-based alloys such as gold, platinum and palladium-based metallic solid glasses, early transition metal-based alloys such as titanium or zirconium-based metallic solid glasses, late transition metal-based systems, e.g. based on Copper, nickel or iron, but also systems based on rare earth metals, such as neodymium or terbium.
- precious metal-based alloys such as gold, platinum and palladium-based metallic solid glasses
- early transition metal-based alloys such as titanium or zirconium-based metallic solid glasses
- late transition metal-based systems e.g. based on Copper, nickel or iron, but also systems based on rare earth metals, such as neodymium or terbium.
- Components made of solid metallic glass can be manufactured using casting processes, since the cooling rates required for amorphous solidification can be achieved with these processes.
- In order to obtain amorphous components from a metallic solid glass it is usually necessary to quickly transfer the melt of a solid glass-forming alloy into a casting mold. This filling of the casting mold with the melt is preferably done by injection (injection molding) or suction (suction molding). In this way, the high cooling rates can be achieved and three-dimensional components can be produced from solid metallic glass.
- casting methods such as Injection molding, low manufacturing tolerances can be achieved.
- ingots of the alloy to be processed are required, which serve as a supply of material to be processed and can be melted homogeneously.
- the ingot must have a sufficient volume so that material is sufficiently available for the entire cast component and also the additional areas of the mold (the sprue; engl sprue.) Can be filled. Therefore, the largest possible ingots are desirable.
- a homogeneous alloy that forms solid glass is first produced.
- the individual components are mixed together and heated above the melting point so that a homogeneous alloy is created.
- the individual components can be melted, for example, in an electric arc or by means of inductive heating.
- the homogeneous alloy is then poured into molds and cooled, creating an ingot.
- these ingots are in the form of cylindrical rods.
- the ingots In order for the ingots to contain enough material to completely fill the casting mold for a casting process for a three-dimensional component, the ingots must be sufficiently dimensioned.
- Typical diameters of cylindrical ingots made of solid glass-forming alloys are in the range of about 20 mm.
- the length of an ingot is preferably at least 3 cm.
- One object of the present invention was to provide an ingot made of a solid glass-forming alloy with a high critical casting thickness, which does not crack during the manufacturing process and can be heated up more quickly during further thermal processing, such as injection molding.
- the object of the invention was to provide a method for producing an ingot from a solid glass-forming alloy with a high critical casting thickness which does not crack during the production process.
- Another object of the invention was to provide ingots made from solid glass-forming alloys which can be heated up more quickly than conventional ingots.
- a solid glass-forming alloy is preferably to be understood as an alloy with a critical casting thickness of at least one millimeter. This means that such an alloy can solidify amorphously up to a thickness of one millimeter at a suitable cooling rate.
- the solid glass-forming alloy preferably has a critical casting thickness of at least 5 mm, in particular of at least 7 mm and completely particularly preferably of at least 10 mm.
- the critical casting thickness is a measure of how easy or difficult a metallic alloy can be brought into the glass state.
- the alloy to be measured is processed into a homogeneous melt in an electric arc and then poured into a water-cooled copper casting mold (also called a permanent mold).
- the mass of the copper casting mold is preferably at least 7 times greater than the mass of the molten mass of the alloy to be determined.
- the temperature of the homogeneous melt before pouring is preferably at least 200 ° C., in particular 300 ° C. and very particularly preferably at least 400 ° C. above the melting temperature.
- the temperature of the copper mold is 20 ° C.
- cylindrical molded parts with increasing diameters are cast at a distance of 1 mm (e.g.
- the cylindrical molded parts produced are examined for their crystalline content by means of dynamic differential scanning calorimetry (DSC).
- DSC dynamic differential scanning calorimetry
- the critical casting thickness is given as the cylinder diameter, which is one millimeter smaller than the cylinder diameter at which the formation of a crystalline phase is first measured using DSC.
- DSC method 2 was used as described herein.
- a homogeneous melt of a solid glass-forming alloy is provided.
- the homogeneous melt is preferably provided by melting the individual elements of the alloy together.
- the individual elements are preferably melted in an electric arc or by means of inductive heating.
- the temperature of the homogeneous melt is preferably at least 200 ° C., in particular at least 300 ° C., and very particularly preferably at least 400 ° C. above the melting temperature of the respective solid glass-forming alloy.
- the temperature of the melt, measured in degrees Celsius is at least 20%, in particular at least 50%, above the melting temperature of the alloy, since this enables particularly stable ingots to be produced.
- step b) the homogeneous melt is poured into a casting mold.
- the casting mold is preferably cylindrical.
- the volume of the casting mold to be filled preferably has dimensions which are greater in all three spatial directions than the critical casting thickness of the solid glass-forming alloy.
- the material of the casting mold can preferably be selected from steel, titanium, copper, ceramic or graphite.
- the mold preferably has a device with which the mold can be actively heated and / or cooled. In one embodiment of the invention, the casting mold can be actively heated, for example by electrical heating.
- the ratio between the weight of the casting mold and the weight of the melt is preferably in the range of 7: 1 or more, particularly preferably in the range of 10: 1 or more.
- the casting mold can be coated in the area that comes into contact with the melt.
- the material of this coating of the casting mold is preferably selected from the group consisting of boron nitride, aluminum oxide (eg Al 2 O 3 ) and yttrium oxide (eg Y 2 O 3 ).
- the coating preferably has or consists of a powder.
- the thickness of the coating, in particular the powder coating can in one embodiment be in the range of 10-50 ⁇ m.
- a powder layer can have an advantageous effect on the mechanical properties of the ingot to be produced.
- the coating can serve, among other things, to more easily remove the ingot from the casting mold.
- the casting mold does not cool below the glass-forming temperature of the solid glass-forming alloy at the contact surface with the melt for at least 5 seconds, in particular for at least 10 seconds and very particularly preferably for at least 30 seconds.
- a melt is also used after the liquid melt has been transferred into the casting mold, even if the solidification process has already started and the solid glass-forming alloy is partially or completely solid as long as the glass transition temperature has not yet fallen below.
- the casting mold does not cool down below the glass formation temperature of the solid glass-forming alloy at any point on the contact surface with the melt for the specified duration.
- the determination of the glass formation temperature of the alloy is described under "Methods".
- the temperature of the casting mold at the contact surface with the melt for the aforementioned duration is at least 10 ° C, in particular at least 20 ° C and particularly preferably at least 40 ° C or at least 80 ° C above the glass formation temperature of the solid glass forming Alloy.
- a temperature measuring probe can be inserted into the casting mold in such a way that it extends to the contact surface of the casting mold with the melt and measures there.
- the temperature measurement is preferably carried out at the point halfway along the longest dimension of the ingot.
- the temperature of the casting mold before it is filled with the melt is preferably set so that the temperature of the casting mold after casting on the contact surface with the melt for at least 5 seconds, in particular for at least 10 seconds and very particularly preferably for at least 30 seconds after contact does not drop below the glass formation temperature of the alloy with the casting mold.
- the casting mold is preferably heated prior to contact with the melt.
- the preferably set temperature of the casting mold directly before pouring the melt is at least 250.degree. C., in particular at least 400.degree. C. and particularly preferably at least 500.degree.
- the casting mold can be heated in an oven, for example.
- the mold can be actively heated, e.g. by electrical heating.
- substantially above the standard atmospheric pressure can be understood to mean an excess pressure of 1 bar or more.
- step c) the melt is cooled to below the glass transition temperature of the solid glass-forming alloy while retaining the ingot (20).
- the melt is preferably cooled down to room temperature.
- the cooling rate in step c) is not restricted further according to the invention.
- the melt is allowed to cool to room temperature without additional action (heating or cooling).
- the melt can be actively cooled below the glass transition temperature in order to accelerate the process.
- an ingot can be produced from an alloy which forms solid glass and which does not shatter during the production process. Furthermore, the method can be used to produce an ingot which does not crack if it is heated to the melting temperature of the alloy within a maximum of 50 seconds. In particular, an ingot can be produced that does not shatter if it falls three times from a height of 30 cm onto a flat, horizontal steel surface. In particular, the method can be used to produce an ingot which does not have an amorphous layer on the surface. The absence of an amorphous layer can be determined under a light microscope.
- the invention relates to an ingot of a solid glass-forming alloy, wherein the alloy has a critical casting thickness of at least 5 mm, and wherein the ingot has an extension in all three spatial directions that is greater than the critical casting thickness, characterized in that that the ingot has a crystalline fraction of at least 90% by weight, in particular at least 95% by weight and particularly preferably at least 98% by weight, measured by means of DSC.
- the critical casting thickness of the alloy is preferably at least 7 mm and in particular at least 10 mm.
- the ingot according to the invention can be produced using the method described herein become.
- the ingot according to the invention does not have an amorphous layer on the surface.
- the term “no amorphous layer” can be understood as a layer that is not thicker than 200 ⁇ m, in particular not thicker than 100 ⁇ m and very particularly preferably not thicker than 50 ⁇ m.
- the absence of an amorphous layer can preferably lead to a reduction in internal stresses in the ingot.
- the absence of an amorphous layer on the surface of the ingot can be determined by means of optical microscopy (incident light microscope).
- FIG. 11 shows a microscopic image of a cross section through an ingot which has amorphous regions. These amorphous areas can be seen as light areas towards the edge (arrow 1). The inner area of the examined ingot has no light areas (arrow 2). Against it shows Figure 2 a microscopic image of a cross-section through an ingot that has no amorphous areas.
- Figure 3 shows a metallurgical micrograph of the sample Figure 2 in higher magnification.
- the polycrystalline structures and their grain boundaries are clearly recognizable.
- the crystalline structure of the ingot according to the invention extends to the edge, which confirms the absence of an amorphous phase (for example in the circled area). If an amorphous phase were to occur, this would preferably develop at the edge first, since the cooling rates can potentially be highest here.
- the total volume of the amorphous layer on the ingot can be 5% or less, in particular 3% or less.
- the crystallinity of the ingot can be measured using differential scanning calorimetry (DSC).
- the ingot is preferably solid and has no cavities, such as, for example, air pockets.
- the shape of the ingot is not limited.
- the ingot can have a cylindrical shape.
- the cylinder diameter preferably has a value of at least 5 mm, in particular at least 15 mm and very particularly preferably at least 25 mm, in each case under the condition that the diameter is greater than the critical casting thickness of the solid glass-forming alloy.
- the length of the cylinder is preferably at least 3 cm.
- the invention relates to a method for producing three-dimensional components from solid metallic glasses by means of casting processes, in particular injection molding, using the inventive ingot of an alloy that forms solid glass.
- the ingot according to the invention is melted into a homogeneous melt (30).
- the complete melting of the ingot (20) preferably takes no longer than 60 seconds, in particular no longer than 40 seconds, and very particularly preferably no longer than 20 seconds, with the ingot being able to be heated without cracking.
- the heating time for already known ingots of the same size is typically in the range of 80 seconds.
- the homogeneous melt (30) is poured, in particular injected, into the casting mold for a three-dimensional component (40).
- the casting mold for producing the three-dimensional component by means of a casting process is preferably dimensioned such that it does not exceed the critical casting thickness of the alloy used at any point, since completely amorphous, three-dimensional components can be produced in this way.
- the ingot can be used to manufacture three-dimensional components that can be manufactured with a high throughput in an injection molding machine.
- the XRD measurements are carried out in accordance with DIN EN 13925-1: 2003-07 and DIN EN 13925-2: 2003-07.
- a cross-section of the material to be examined is made with a diamond saw.
- the flat surface of the cross-section is in the region of approx. 1 cm 2 .
- the general measurement details used are summarized as follows: Diffraction: Bragg-Brentano; Detector: scintillation counter; Radiation: Cu K ⁇ 1.5406 ⁇ ; Source: 40 kV, 25 mA; Measurement method: reflection.
- the empty sample holder is measured first to determine the background signal. This background measurement is subtracted from all subsequent measurements of the samples to be examined.
- Discrete diffraction signals in the diffractogram can be evaluated according to the Debye-Scherrer method using the Bragg equation. When become visible from discrete, crystalline peaks above the statistical noise, a crystalline proportion of at least 5% by weight is assumed. If no sharp diffraction signals can be determined in the diffraction pattern, the crystalline portion is below 5%.
- the DSC measurements within the scope of the invention are carried out in accordance with DIN EN ISO 11357-1: 2017-02 and DIN EN ISO 11357-3: 2018-07.
- the sample to be measured in the form of a thin disk or film (approx. 80-100 mg) is placed in the measuring device (NETZSCH DSC 404F1, NETZSCH GmbH, Germany).
- the heating rate is 20.0 K / min.
- Al 2 O 3 is used as the crucible material.
- the heat flow is measured against an empty reference crucible, so that only the thermal behavior of the sample is measured.
- Samples that are expected to be predominantly crystalline and have only a small amount of amorphous phase are measured according to the measurement method given above.
- the complete crystallinity of the sample after running through the measurement process can also be confirmed by means of XRD, through the absence of broad, unspecific signals in the diffraction diagram, which would indicate an amorphous phase.
- the amorphous proportion of samples with more than 5% by weight can be determined by comparing the enthalpy of crystallization of the unknown sample with the value for the completely amorphous sample from DSC method 2) (see below).
- a sample of each of the cast cylinders is measured using DSC. As long as the diameter of the cylinder is below the critical casting thickness, the sample is completely amorphous before the start of the measurement and crystallizes during the DSC measurement in step a) of the measurement process.
- the enthalpy of crystallization of the alloy is determined from the measurement of the completely amorphous material. The enthalpy of crystallization is determined for all samples with increasing cylinder diameter. The specific enthalpy of crystallization for samples whose cylinder diameter is below the critical casting thickness is constant within the scope of the measurement inaccuracy.
- the critical casting thickness is determined as the cylinder diameter up to which the enthalpy of crystallization is constant with increasing diameter.
- step a) the amorphous sample is crystallized.
- step c) the thermal behavior of the already completely crystallized sample is recorded.
- the measurement from step c) is subtracted from the measurement from step a).
- the resulting curve includes an endothermic transition at a lower temperature and an exothermic signal at a higher temperature.
- the signal at a higher temperature corresponds to the crystallization process.
- the endothermic signal corresponds to the glass transition.
- a tangent line to the baseline is determined in front of the glass transition area (by linear fitting).
- a second tangent is determined at the point of inflection (corresponding to the peak value of the first derivative over time) of the glass transition region.
- the temperature value at the intersection of the two tangents indicates the glass transition temperature (T f according to AST; 1356-03).
- the individual components were melted under protective gas by means of inductive melting to form a homogeneous alloy with the composition Zr 52.5 Ti 5 Cu 17.9 Ni 14.6 Al 10 .
- This alloy has a glass transition temperature of 403 ° C.
- 80 g of the homogeneous alloy were brought to a temperature above the melting temperature of the alloy (805 ° C.) by means of inductive heating in a crucible.
- Table 1 shows the temperatures of the respective melt for the respective experiment.
- the casting mold was preheated to a temperature defined in Table 1 in an oven.
- the respective homogeneous melt according to Table 1 was then poured into a casting mold.
- the mold had a cylindrical shape with an inner diameter of 19 mm. The temperature of the melt was measured continuously after the cylindrical casting mold had been filled.
- the measured values for the temperature of the melt after 10 seconds in the casting mold can be read off in Table 1.
- Table 1 Table 1
- Examples 1 and 2 in Table 1 are comparative examples, Examples 3-5 are examples according to the invention.
- the quality of the cast ingots was assessed according to the following criteria: Cast parts of poor quality shatter as soon as they cool in the mold. Good quality cast ingots remain intact if they are heated to the melting temperature within 50 seconds or less with an output of 5 kW. Very good quality ingots also withstand a drop test from a height of 30 cm onto a flat steel plate three times in a row without cracking. It is clear from Examples 1-5 that ingots in which the temperature of the melt was above the glass transition temperature after 10 seconds were significantly more robust than ingots in which the temperature of the melt was below.
Abstract
Verfahren zur Herstellung eines Ingots einer Massivglas-bildenden Legierung, aufweisend die Schritte: Bereitstellen einer homogenen Schmelze einer Massivglas-bildenden Legierung, Gießen der homogenen Schmelze in eine Gussform, wobei die Gussform an der Kontaktfläche mit der Schmelze mindestens 5 Sekunden nicht unter die Glasbildungstemperatur der Legierung abkühlt, und Abkühlen der Schmelze unter die Glasübergangstemperatur der Massivglas-bildenden Legierung unter Erhalt des Ingots.A method for producing an ingot of a solid glass-forming alloy, comprising the steps: providing a homogeneous melt of a solid glass-forming alloy, pouring the homogeneous melt into a casting mold, the casting mold at the contact surface with the melt not falling below the glass-forming temperature for at least 5 seconds Alloy cools, and cooling of the melt below the glass transition temperature of the solid glass-forming alloy to obtain the ingot.
Description
Die Erfindung betrifft ein Verfahren zur Herstellung von mechanisch und thermisch stabilen Ingots (auch Vorform genannt) aus Legierungen, die ein metallisches Massivglas bilden können. Weiterhin betrifft die Erfindung einen Ingot einer Massivglas-bildenden Legierung, der mit dem erfindungsgemäßen Verfahren hergestellt wird und die Verwendung dieses Ingots in einem Gussverfahren.The invention relates to a method for the production of mechanically and thermally stable ingots (also called preforms) from alloys which can form a metallic solid glass. The invention further relates to an ingot of a solid glass-forming alloy which is produced using the method according to the invention and the use of this ingot in a casting process.
Seit ihrer Entdeckung vor etwa 50 Jahren am California Institute of Technology sind metallische Gläser Gegenstand umfangreicher Forschung. Im Laufe der Jahre gelang es, die Prozessierbarkeit und Eigenschaften dieser Materialklasse kontinuierlich zu verbessern. Waren die ersten metallischen Gläser noch einfache, binäre (aus zwei Komponenten aufgebaute) Legierungen, deren Herstellung Abkühlraten im Bereich von 106 Kelvin pro Sekunde (K/s) erforderten, lassen sich neuere, komplexere Legierungen bereits bei deutlich geringeren Abkühlraten im Bereich einiger K/s in den Glaszustand überführen. Dies hat erheblichen Einfluss auf die Prozessführung sowie die realisierbaren Bauteile. Die Abkühlgeschwindigkeit, ab der eine Kristallisation der Schmelze ausbleibt und die Schmelze als Glas erstarrt, wird als kritische Abkühlrate bezeichnet. Sie ist eine systemspezifische, stark von der Zusammensetzung der Schmelze abhängige Größe, welche zudem die maximal erreichbaren Bauteildicken festlegt. Bedenkt man, dass die in der Schmelze gespeicherte Wärmeenergie ausreichend schnell durch das System abtransportiert werden muss, wird klar, dass sich aus Systemen mit hohen kritischen Abkühlraten lediglich Bauteile mit geringer Dicke fertigen lassen. Anfänglich wurden metallische Gläser daher meist nach dem Schmelzspinnverfahren (Englisch: melt spinning) hergestellt. Die Schmelze wird hierbei auf ein rotierendes Kupferrad abgestreift und erstarrt glasartig in Form von dünnen Bändern bzw. Folien mit Dicken im Bereich einiger hundertstel bis zehntel Millimeter. Durch die Entwicklung neuer, komplexer Legierungen mit deutlich geringeren kritischen Abkühlraten, können zunehmend andere Herstellungsverfahren genutzt werden. Heutige glasbildende metallische Legierungen lassen sich bereits durch Gießen einer Schmelze in gekühlte Kupferkokillen in den Glaszustand überführen. Die realisierbaren Bauteildicken liegen dabei legierungsspezifisch im Bereich einiger Millimeter bis Zentimeter. Derartige Legierungen werden als metallische Massivgläser (Englisch: Bulk Metallic Glasses, BMG) bezeichnet. Im Rahmen der vorliegenden Erfindung ist unter einem metallischen Massivglas ein Material mit einer kritischen Gussdicke von mindestens einem Millimeter zu verstehen. Heutzutage ist eine Vielzahl solcher Legierungssysteme bekannt. Ihre Unterteilung erfolgt gewöhnlich anhand der Zusammensetzung, wobei man das Legierungselement mit dem höchsten Gewichtsanteil als Basiselement bezeichnet. Die bestehenden Systeme umfassen unter anderem Edelmetall-basierte Legierungen wie bspw. Gold-, Platin, und Palladium-basierte metallische Massivgläser, frühe Übergangsmetall basierte Legierungen wie z.B. Titan- oder Zirkonium-basierte metallische Massivgläser, späte Übergangsmetall-basierte Systeme, z.B. auf Basis von Kupfer-, Nickel-oder Eisen, aber auch Systeme auf Basis von Seltenerdmetallen, z.B. Neodym oder Terbium.Metallic glasses have been the subject of extensive research since their discovery at the California Institute of Technology about 50 years ago. Over the years it has been possible to continuously improve the processability and properties of this class of materials. While the first metallic glasses were still simple, binary alloys (made up of two components), the production of which required cooling rates in the range of 10 6 Kelvin per second (K / s), newer, more complex alloys can already be produced at significantly lower cooling rates in the range of a few K. / s in the glass state. This has a significant impact on process management and the components that can be implemented. The cooling rate at which the melt does not crystallize and the melt solidifies as glass is referred to as the critical cooling rate. It is a system-specific variable that is heavily dependent on the composition of the melt, which also defines the maximum component thickness that can be achieved. If one considers that the thermal energy stored in the melt has to be transported away through the system sufficiently quickly, it becomes clear that only components with a small thickness can be manufactured from systems with high critical cooling rates. In the beginning, metallic glasses were therefore mostly produced using the melt spinning process. The melt is stripped onto a rotating copper wheel and solidifies like a glass in the form of thin strips or foils with thicknesses in the range of a few hundredths to tenths of a millimeter. Due to the development of new, complex alloys with significantly lower critical cooling rates, other manufacturing processes can increasingly be used. Today's glass-forming metallic alloys can be converted into the glass state by pouring a melt into cooled copper molds. The realizable component thicknesses are alloy-specific in the range of a few millimeters to centimeters. Such alloys are called solid metallic glasses (English: Bulk Metallic Glasses, BMG). In the context of the present invention, a metallic solid glass is to be understood as a material with a critical casting thickness of at least one millimeter. A large number of such alloy systems are known today. They are usually subdivided on the basis of their composition, with the alloy element with the highest weight percentage being called the base element. The existing systems include precious metal-based alloys such as gold, platinum and palladium-based metallic solid glasses, early transition metal-based alloys such as titanium or zirconium-based metallic solid glasses, late transition metal-based systems, e.g. based on Copper, nickel or iron, but also systems based on rare earth metals, such as neodymium or terbium.
Metallische Massivgläser weisen im Vergleich zu klassischen, kristallinen Metallen typischer Weise mindestens eine der folgenden Eigenschaften auf:
- eine höhere spezifische Festigkeit, was zum Beispiel dünnere Wandstärken ermöglicht,
- eine höhere Härte, wodurch die Oberflächen besonders kratzfest sein können,
- eine viel höhere elastische Dehnbarkeiten und Resilienzen,
- eine thermoplastische Formbarkeit und
- eine höhere Korrosionsbeständigkeit.
- a higher specific strength, which enables, for example, thinner wall thicknesses,
- higher hardness, which means that the surfaces can be particularly scratch-resistant,
- much higher elastic extensibility and resilience,
- thermoplastic moldability and
- a higher corrosion resistance.
Bauteile aus metallischen Massivgläser können mittels Gussverfahren hergestellt werden, da bei diesen Verfahren die notwendigen Abkühlraten für ein amorphes Erstarren erreicht werden können. Um amorphe Bauteile aus einem metallischen Massivglas zu erhalten, ist es meist erforderlich die Schmelze einer Massivglas-bildendenden Legierung zügig in eine Gussform zu überführen. Bevorzugt geschieht dieses Füllen der Gussform mit der Schmelze durch Einspritzen (Spritzguss) oder Einsaugen (Saugguss). Auf diese Weise können die hohen Abkühlraten erreicht werden und dreidimensionale Bauteile aus metallischen Massivgläsern hergestellt werden. Durch die Verwendung von Gussverfahren, wie z.B. Spritzguss, können geringe Fertigungstoleranzen erreicht werden.Components made of solid metallic glass can be manufactured using casting processes, since the cooling rates required for amorphous solidification can be achieved with these processes. In order to obtain amorphous components from a metallic solid glass, it is usually necessary to quickly transfer the melt of a solid glass-forming alloy into a casting mold. This filling of the casting mold with the melt is preferably done by injection (injection molding) or suction (suction molding). In this way, the high cooling rates can be achieved and three-dimensional components can be produced from solid metallic glass. By using casting methods such as Injection molding, low manufacturing tolerances can be achieved.
Für Gussverfahren sind Ingots der zu verarbeitenden Legierung notwendig, die als Vorrat an zu verarbeitendem Material dienen und homogen aufgeschmolzen werden können. Dazu müssen die Ingots ein ausreichendes Volumen aufweisen, damit genügend Material für das gesamte gegossene Bauteil verfügbar ist und auch die zusätzlichen Räume der Gussform (den Anguss; engl. sprue) ausgefüllt werden können. Daher sind möglichst große Ingots wünschenswert.For casting processes, ingots of the alloy to be processed are required, which serve as a supply of material to be processed and can be melted homogeneously. For this, the ingot must have a sufficient volume so that material is sufficiently available for the entire cast component and also the additional areas of the mold (the sprue; engl sprue.) Can be filled. Therefore, the largest possible ingots are desirable.
Zur Herstellung von Ingots aus Massivglas-bildenden Legierungen wird zuerst eine homogene, Massivglas-bildende Legierung hergestellt. Hierzu werden die Einzelkomponenten zusammengemischt und über den Schmelzpunkt erhitzt, sodass eine homogene Legierung entsteht. Das Aufschmelzen der Einzelkomponenten kann zum Beispiel im Lichtbogen oder mittels induktivem Heizen erfolgen. Die homogene Legierung wird anschließend in Gussformen gefüllt und abgekühlt, wodurch ein Ingot entsteht. Im Allgemeinen haben diese Ingots die Form von zylindrischen Stäben. Damit die Ingots genügend Material enthalten, um die Gussform für ein Gussverfahren für ein dreidimensionales Bauteil vollständig auszufüllen, müssen die Ingots ausreichend dimensioniert sein. Typische Durchmesser von zylindrischen Ingots aus Massivglas-bildenden Legierungen liegen im Bereich von etwa 20 mm. Die Länge eines Ingots beträgt bevorzugt mindestens 3 cm.To produce ingots from alloys that form solid glass, a homogeneous alloy that forms solid glass is first produced. For this purpose, the individual components are mixed together and heated above the melting point so that a homogeneous alloy is created. The individual components can be melted, for example, in an electric arc or by means of inductive heating. The homogeneous alloy is then poured into molds and cooled, creating an ingot. Generally, these ingots are in the form of cylindrical rods. In order for the ingots to contain enough material to completely fill the casting mold for a casting process for a three-dimensional component, the ingots must be sufficiently dimensioned. Typical diameters of cylindrical ingots made of solid glass-forming alloys are in the range of about 20 mm. The length of an ingot is preferably at least 3 cm.
Aus
Die Herstellung von qualitativ hochwertigen Ingots aus Materialien mit einer hohen kritischen Gussdicke und mit Abmessungen größer als die kritische Gussdicke, ist schwierig. Zum einen gibt es bei der Herstellung erheblichen Ausschuss, da bekannte Ingots häufig bereits im Herstellungsverfahren zerspringen. Zum anderen zerspringen die herkömmlich hergestellten Ingots teilweise beim Transport oder beim Aufheizen während des eigentlichen Herstellungsschritts eines dreidimensionalen Bauteils mittels Gussverfahren. Wenn die Ingots während der Herstellung eines dreidimensionalen Bauteils zerspringen, ist dies nachteilig, weil die Wärmeleitung durch die Risse unterbrochen wird. Dadurch erhöht sich die Prozessdauer für die Herstellung von dreidimensionalen Bauteilen. Um das Zerspringen von herkömmlichen Ingots, die den Herstellungsprozess unbeschadet überstanden haben, zu vermeiden, muss der Ingot sehr langsam auf die Schmelztemperatur aufgeheizt werden. Typischer Weise dauert das Schmelzen der Ingots mindestens 80 Sekunden.The production of high quality ingots from materials with a high critical casting thickness and with dimensions larger than the critical casting thickness is difficult. On the one hand, there is considerable scrap during manufacture, since known ingots often burst during the manufacturing process. On the other hand, the conventionally manufactured ingots sometimes shatter during transport or during heating during the actual manufacturing step of a three-dimensional component using the casting process. If the ingots burst during the production of a three-dimensional component, this is disadvantageous because the heat conduction is interrupted by the cracks. This increases the process time for the production of three-dimensional components. In order to avoid the shattering of conventional ingots, which survived the manufacturing process undamaged, the ingot must be heated very slowly to the melting temperature. It typically takes at least 80 seconds to melt the ingots.
Eine Aufgabe der vorliegenden Erfindung bestand in der Bereitstellung eines Ingots aus einer Massivglas-bildenden Legierung mit hoher kritischer Gussdicke, der während des Herstellungsverfahrens nicht zerspringt und bei der thermischen Weiterverarbeitung, wie z.B. dem Spritzguss, schneller aufgeheizt werden kann.One object of the present invention was to provide an ingot made of a solid glass-forming alloy with a high critical casting thickness, which does not crack during the manufacturing process and can be heated up more quickly during further thermal processing, such as injection molding.
Weiterhin bestand die Aufgabe der Erfindung in der Bereitstellung eines Verfahrens zur Herstellung eines Ingots aus einer Massivglas-bildenden Legierung mit hoher kritischer Gussdicke, der während des Herstellungsverfahrens nicht zerspringt.Furthermore, the object of the invention was to provide a method for producing an ingot from a solid glass-forming alloy with a high critical casting thickness which does not crack during the production process.
Eine weitere Aufgabe der Erfindung war die Bereitstellung von Ingots aus Massivglas-bildenden Legierungen, die schneller aufgeheizt werden können als herkömmliche Ingots.Another object of the invention was to provide ingots made from solid glass-forming alloys which can be heated up more quickly than conventional ingots.
Ein Beitrag zur Lösung mindestens einer der genannten Aufgaben wird geleistet durch die Gegenstände der unabhängigen Ansprüche.A contribution to solving at least one of the tasks mentioned is made by the subjects of the independent claims.
Ein erster Aspekt der Erfindung betrifft ein Verfahren zur Herstellung eines Ingots (20) einer Massivglas-bildenden Legierung, aufweisend die Schritte:
- a. Bereitstellen einer homogenen Schmelze (10) einer Massivglas-bildenden Legierung,
- b. Gießen der homogenen Schmelze in eine Gussform, wobei die Gussform an der Kontaktfläche mit
der Schmelze mindestens 5 Sekunden nicht unter die Glasbildungstemperatur der Legierung abkühlt, und - c. Abkühlen der Schmelze unter die Glasübergangstemperatur der Massivglas-bildenden Legierung unter Erhalt des Ingots (20).
- a. Providing a homogeneous melt (10) of a solid glass-forming alloy,
- b. Pouring the homogeneous melt into a casting mold, the casting mold not cooling below the glass-forming temperature of the alloy at the contact surface with the melt for at least 5 seconds, and
- c. Cooling of the melt below the glass transition temperature of the solid glass-forming alloy to obtain the ingot (20).
Die Massivglas-bildenden Legierung ist in ihrer Zusammensetzung erfindungsgemäß nicht weiter beschränkt. Bevorzugt ist unter einer Massivglas-bildenden Legierung eine Legierung mit einer kritischen Gussdicke von mindestens einem Millimeter zu verstehen. Das bedeutet, dass eine solche Legierung bei geeignet Abkühlrate bis zu einer Dicke von einem Millimeter amorph erstarren kann.The composition of the solid glass-forming alloy is not restricted further according to the invention. A solid glass-forming alloy is preferably to be understood as an alloy with a critical casting thickness of at least one millimeter. This means that such an alloy can solidify amorphously up to a thickness of one millimeter at a suitable cooling rate.
Unter Massivglas-bildenden Legierungen sind solche zu verstehen, die unter bestimmten thermischen Bedingungen im festen Zustand metallischen Bindungscharakter und gleichzeitig eine amorphe, also nicht-kristalline, Phase aufweisen können. Die Legierung kann auf unterschiedlichen Elementen basieren. "Basiert" meint in diesem Zusammenhang, dass das jeweils genannte Element, auf das Gewicht der Legierung bezogen, den größten Anteil darstellt. Bestandteile, die bevorzugt auch die Basis der Legierung stellen, können beispielsweise ausgewählt sein aus:
- A. Metallen aus Gruppe IA und IIA des Periodensystems, z.B. Magnesium, Calcium,
- B. Metallen aus Gruppe IIIA und IVA, z.B. Aluminium oder Gallium,
- C. frühen Übergangsmetallen aus den Gruppen IVB bis VIIIB, wie z.B. Titan, Zirkon, Hafnium, Niob, Tantal, Chrom, Molybdän, Mangan,
- D. späten Übergangsmetallen aus den Gruppen VIIIB, IB, IIB, wie z.B. Eisen, Kobalt, Nickel, Kupfer, Palladium, Platin, Gold, Silber, Zink,
- E. Seltenerdmetallen, wie z.B. Scandium, Yttrium, Terbium, Lanthan, Cer, Neodym. Gadolinium und
- F. Nichtmetallen, wie z.B. Bor, Kohlenstoff, Phosphor, Silizium, Germanium, Schwefel Bevorzugte Kombinationen von Elementen in metallischen Massivgläser sind ausgewählt aus:
- späten Übergangsmetallen und Nichtmetallen, wobei das späte Übergangsmetall die Basis darstellt, beispielsweise Ni-P, Pd-Si, Au-Si-Ge, Pd-Ni-Cu-P, Fe-Cr-Mo-P-C-B,
- frühen und späten Übergangsmetallen, wobei beide Metalle die Basis darstellen können, wie z.B. Zr-Cu, Zr-Ni, Ti-Ni, Zr-Cu-Ni-Al, Zr-Ti-Cu-Ni-Be,
- Metalle aus Gruppe B mit Seltenerdmetallen, wobei das Metall B die Basis darstellt, wie z.B. Al-La, Al-Ce, Al-La-Ni-Co, La-(Al/Ga)-Cu-Ni, und
- Metalle aus Gruppe A mit späten Übergangsmetallen, wobei das Metall A die Basis darstellt, wie z.B. Mg-Cu, Ca-Mg-Zn, Ca-Mg-Cu
- A. Metals from group IA and IIA of the periodic table, e.g. magnesium, calcium,
- B. Metals from group IIIA and IVA, e.g. aluminum or gallium,
- C. early transition metals from groups IVB to VIIIB, such as titanium, zircon, hafnium, niobium, tantalum, chromium, molybdenum, manganese,
- D. late transition metals from groups VIIIB, IB, IIB, such as iron, cobalt, nickel, copper, palladium, platinum, gold, silver, zinc,
- E. Rare earth metals such as scandium, yttrium, terbium, lanthanum, cerium, neodymium. Gadolinium and
- F. Non-metals, such as boron, carbon, phosphorus, silicon, germanium, sulfur Preferred combinations of elements in metallic solid glasses are selected from:
- late transition metals and non-metals, with the late transition metal being the base, e.g. Ni-P, Pd-Si, Au-Si-Ge, Pd-Ni-Cu-P, Fe-Cr-Mo-PCB,
- early and late transition metals, where both metals can represent the basis, such as Zr-Cu, Zr-Ni, Ti-Ni, Zr-Cu-Ni-Al, Zr-Ti-Cu-Ni-Be,
- Metals from group B with rare earth metals, where the metal B is the base, such as Al-La, Al-Ce, Al-La-Ni-Co, La- (Al / Ga) -Cu-Ni, and
- Metals from group A with late transition metals, where the metal A is the base, such as Mg-Cu, Ca-Mg-Zn, Ca-Mg-Cu
Aufgrund der intrinsischen Wärmeleitung des Materials ergibt sich selbst bei maximal erzielbarer Kühlrate eine maximale Gussdicke, welche das Gussstück in mindestens einer Dimension unterschreiten muss, um noch eine homogene amorphe Phase ausbilden zu können. Bevorzugt weist die Massivglas-bildende Legierung eine kritische Gussdicke von mindestens 5 mm, insbesondere von mindestens 7 mm und ganz besonders bevorzugt von mindestens 10 mm auf. Im Rahmen der vorliegenden Erfindung ist die kritische Gussdicke (engl.: maximum casting thickness) ein Maß dafür, wie leicht oder schwer eine metallische Legierung in den Glaszustand gebracht werden kann.Due to the intrinsic heat conduction of the material, even with the maximum achievable cooling rate, there is a maximum casting thickness which the casting must be less than in at least one dimension in order to still be able to form a homogeneous amorphous phase. The solid glass-forming alloy preferably has a critical casting thickness of at least 5 mm, in particular of at least 7 mm and completely particularly preferably of at least 10 mm. In the context of the present invention, the critical casting thickness ( maximum casting thickness ) is a measure of how easy or difficult a metallic alloy can be brought into the glass state.
Um die kritische Gussdicke im Rahmen der Erfindung zu bestimmen, wird die zu vermessende Legierung im Lichtbogen zu einer homogenen Schmelze verarbeitet und anschließend in eine wassergekühlte Kupfergussform (auch Kokille genannt) abgegossen. Die Masse der Kupfergussform ist bevorzugt mindestens um den Faktor 7 größer als die Masse der eingefüllten Schmelze der zu bestimmenden Legierung. Die Temperatur der homogenen Schmelze vor dem Gießen liegt bevorzugt mindestens 200°C, insbesondere 300°C und ganz besonders bevorzugt mindestens 400°C über der Schmelztemperatur. Die Temperatur der Kupfergussform beträgt 20°C. Zur Bestimmung der kritischen Gussdicke werden zylindrische Formteile mit aufsteigenden Durchmessern im Abstand von 1 mm gegossen (z.B. 2mm, 3mm, 4 mm, 5 mm, 6 mm, usw.). Die erzeugten zylindrischen Formteile werden mittels dynamischer Differenzkalorimetrie (differential scanning calorimetry, DSC) auf ihren kristallinen Anteil untersucht. Als kritische Gussdicke wird der Zylinderdurchmesser angegeben, der einen Millimeter kleiner ist als der Zylinderdurchmesser, bei dem zuerst die Bildung einer kristallinen Phase mittels DSC gemessen wird. Zur Bestimmung der Anwesenheit einer kristallinen Phase wurde das DSC-Verfahren 2) angewendet, so wie es hierin beschrieben ist.In order to determine the critical casting thickness within the scope of the invention, the alloy to be measured is processed into a homogeneous melt in an electric arc and then poured into a water-cooled copper casting mold (also called a permanent mold). The mass of the copper casting mold is preferably at least 7 times greater than the mass of the molten mass of the alloy to be determined. The temperature of the homogeneous melt before pouring is preferably at least 200 ° C., in particular 300 ° C. and very particularly preferably at least 400 ° C. above the melting temperature. The temperature of the copper mold is 20 ° C. To determine the critical casting thickness, cylindrical molded parts with increasing diameters are cast at a distance of 1 mm (e.g. 2 mm, 3 mm, 4 mm, 5 mm, 6 mm, etc.). The cylindrical molded parts produced are examined for their crystalline content by means of dynamic differential scanning calorimetry (DSC). The critical casting thickness is given as the cylinder diameter, which is one millimeter smaller than the cylinder diameter at which the formation of a crystalline phase is first measured using DSC. To determine the presence of a crystalline phase, DSC method 2) was used as described herein.
In Schritt a) der vorliegenden Erfindung wird eine homogene Schmelze einer Massivglas-bildenden Legierung bereitgestellt. Das Bereitstellen der homogenen Schmelze erfolgt bevorzugt durch Zusammenschmelzen der einzelnen Elemente der Legierung. Das Schmelzen der einzelnen Elemente erfolgt bevorzugt im Lichtbogen oder mittels induktiven Heizens. Die Temperatur der homogenen Schmelze liegt bevorzugt mindestens 200°C, insbesondere mindestens 300°C, und ganz besonders bevorzugt mindestens 400°C über der Schmelztemperatur der jeweiligen Massivglas-bildenden Legierung. In einer bevorzugten Ausführung liegt die Temperatur der Schmelze, gemessen in Grad Celsius, mindestens 20%, insbesondere mindestens 50% über der Schmelztemperatur der Legierung, da dadurch besonders stabile Ingots erzeugt werden können.In step a) of the present invention, a homogeneous melt of a solid glass-forming alloy is provided. The homogeneous melt is preferably provided by melting the individual elements of the alloy together. The individual elements are preferably melted in an electric arc or by means of inductive heating. The temperature of the homogeneous melt is preferably at least 200 ° C., in particular at least 300 ° C., and very particularly preferably at least 400 ° C. above the melting temperature of the respective solid glass-forming alloy. In a preferred embodiment, the temperature of the melt, measured in degrees Celsius, is at least 20%, in particular at least 50%, above the melting temperature of the alloy, since this enables particularly stable ingots to be produced.
In Schritt b) erfolgt das Gießen der homogenen Schmelze in eine Gussform. Die Gussform ist erfindungsgemäß in ihrer Form nicht weiter beschränkt. Bevorzugt ist die Gussform zylindrisch. Bevorzugt weist das zu füllende Volumen der Gussform Abmessungen auf, die in allen drei Raumrichtungen größer sind als die kritische Gussdicke der Massivglas-bildenden Legierung. Das Material der Gussform kann bevorzugt ausgewählt sein aus Stahl, Titan, Kupfer, Keramik oder Graphit. Bevorzugt weist die Gussform eine Vorrichtung auf, mit der die Gussform aktiv erhitzt und/oder abgekühlt werden kann. In einer Ausführungsform der Erfindung kann die Gussform aktiv geheizt werden, z.B. durch elektrisches Heizen.In step b) the homogeneous melt is poured into a casting mold. According to the invention, the shape of the casting mold is not restricted further. The casting mold is preferably cylindrical. The volume of the casting mold to be filled preferably has dimensions which are greater in all three spatial directions than the critical casting thickness of the solid glass-forming alloy. The material of the casting mold can preferably be selected from steel, titanium, copper, ceramic or graphite. The mold preferably has a device with which the mold can be actively heated and / or cooled. In one embodiment of the invention, the casting mold can be actively heated, for example by electrical heating.
Das Verhältnis zwischen dem Gewicht der Gussform und dem Gewicht der Schmelze liegt bevorzugt im Bereich von 7:1 oder mehr, besonders bevorzugt im Bereich von 10:1 oder mehr. In einer bevorzugten Ausgestaltung der Erfindung kann die Gussform in dem Bereich, der mit der Schmelze in Kontakt kommt, beschichtet sein. Das Material dieser Beschichtung der Gussform ist vorzugsweise ausgewählt, aus der Gruppe bestehend aus Bornitrid, Aluminiumoxid (z.B. Al2O3) und Yttriumoxid (z.B. Y2O3). Bevorzugt weist die Beschichtung ein Pulver auf oder besteht daraus. Die Dicke der Beschichtung, insbesondere der Pulverbeschichtung, kann in einer Ausführung im Bereich von 10 - 50 µm liegen. Eine Pulverschicht kann sich vorteilhaft auf die mechanischen Eigenschaften des herzustellenden Ingots auswirken. Die Beschichtung kann unter anderem dazu dienen, den Ingot leichter aus der Gussform zu entfernen.The ratio between the weight of the casting mold and the weight of the melt is preferably in the range of 7: 1 or more, particularly preferably in the range of 10: 1 or more. In a preferred embodiment of the invention, the casting mold can be coated in the area that comes into contact with the melt. The material of this coating of the casting mold is preferably selected from the group consisting of boron nitride, aluminum oxide (eg Al 2 O 3 ) and yttrium oxide (eg Y 2 O 3 ). The coating preferably has or consists of a powder. The thickness of the coating, in particular the powder coating, can in one embodiment be in the range of 10-50 μm. A powder layer can have an advantageous effect on the mechanical properties of the ingot to be produced. The coating can serve, among other things, to more easily remove the ingot from the casting mold.
Erfindungsgemäß kühlt die Gussform an der Kontaktfläche mit der Schmelze für mindestens 5 Sekunden, insbesondere für mindestens 10 Sekunden und ganz besonders bevorzugt für mindestens 30 Sekunden nicht unter die Glasbildungstemperatur der Massivglas-bildenden Legierung ab. Im Rahmen der Erfindung wird auch noch von einer Schmelze gesprochen, nachdem die flüssige Schmelze in die Gussform überführt wurde, selbst wenn der Erstarrungsprozess bereits eingesetzt hat und die Massivglas-bildende Legierung teilweise oder vollständig fest ist, solange die Glasübergangstemperatur noch nicht unterschritten ist.According to the invention, the casting mold does not cool below the glass-forming temperature of the solid glass-forming alloy at the contact surface with the melt for at least 5 seconds, in particular for at least 10 seconds and very particularly preferably for at least 30 seconds. In the context of the invention, a melt is also used after the liquid melt has been transferred into the casting mold, even if the solidification process has already started and the solid glass-forming alloy is partially or completely solid as long as the glass transition temperature has not yet fallen below.
In bevorzugter Ausbildung der Erfindung kühlt die Gussform für die angegebene Dauer an keiner Stelle der Kontaktfläche mit der Schmelze unter die Glasbildungstemperatur der Massivglas-bildenden Legierung ab. Die Bestimmung der Glasbildungstemperatur der Legierung wird unter "Methoden" beschrieben. In einer bevorzugten Ausführungsform der Erfindung liegt Temperatur der Gussform an der Kontaktfläche mit der Schmelze für die zuvor genannten Dauer mindestens 10°C, insbesondere mindestens 20°C und besonders bevorzugt mindestens 40°C oder mindestens 80°C über der Glasbildungstemperatur der Massivglas-bildenden Legierung.In a preferred embodiment of the invention, the casting mold does not cool down below the glass formation temperature of the solid glass-forming alloy at any point on the contact surface with the melt for the specified duration. The determination of the glass formation temperature of the alloy is described under "Methods". In a preferred embodiment of the invention, the temperature of the casting mold at the contact surface with the melt for the aforementioned duration is at least 10 ° C, in particular at least 20 ° C and particularly preferably at least 40 ° C or at least 80 ° C above the glass formation temperature of the solid glass forming Alloy.
Zur Messung der Temperatur der Gussform an der Kontaktfläche kann eine Temperaturmesssonde in die Gussform so eingelassen sein, dass sie bis an die Kontaktfläche der Gussform mit der Schmelze reicht und dort misst. Die Temperaturmessung erfolgt bevorzugt am Punkt der halben Länge der längsten Ausdehnung des Ingots. Die Temperatur der Gussform vor dem Befüllen mit der Schmelze wird bevorzugt so eingestellt, dass die Temperatur der Gussform nach dem Gießen an der Kontaktfläche mit der Schmelze für mindestens 5 Sekunden, insbesondere für mindestens 10 Sekunden und ganz besonders bevorzugt für mindestens 30 Sekunden nach dem Kontakt mit der Gussform nicht unter die Glasbildungstemperatur der Legierung absinkt.To measure the temperature of the casting mold on the contact surface, a temperature measuring probe can be inserted into the casting mold in such a way that it extends to the contact surface of the casting mold with the melt and measures there. The temperature measurement is preferably carried out at the point halfway along the longest dimension of the ingot. The temperature of the casting mold before it is filled with the melt is preferably set so that the temperature of the casting mold after casting on the contact surface with the melt for at least 5 seconds, in particular for at least 10 seconds and very particularly preferably for at least 30 seconds after contact does not drop below the glass formation temperature of the alloy with the casting mold.
Bevorzugt wird die Gussform vor dem Kontakt mit der Schmelze aufgeheizt. Die bevorzugt eingestellte Temperatur der Gussform direkt vor dem Gießen der Schmelze beträgt mindestens 250°C, insbesondere mindestens 400°C und besonders bevorzugt mindestens 500°C. Das Aufheizen der Gussform kann beispielsweise in einem Ofen erfolgen. Alternativ kann die Gussform aktiv beheizt werden, z.B. durch elektrisches Heizen.The casting mold is preferably heated prior to contact with the melt. The preferably set temperature of the casting mold directly before pouring the melt is at least 250.degree. C., in particular at least 400.degree. C. and particularly preferably at least 500.degree. The casting mold can be heated in an oven, for example. Alternatively, the mold can be actively heated, e.g. by electrical heating.
Bevorzugt wird nach dem Gießen der Schmelze kein zusätzlicher Druck auf die Schmelze ausgeübt, der wesentlich über dem Standardatmosphärendruck liegt. Unter "wesentlich über dem Standardatmosphärendruck" kann im Rahmen der Erfindung ein Überdruck von 1 bar oder mehr verstanden werden.After the melt has been poured, it is preferred that no additional pressure is exerted on the melt which is substantially above the standard atmospheric pressure. In the context of the invention, “substantially above the standard atmospheric pressure” can be understood to mean an excess pressure of 1 bar or more.
In Schritt c) erfolgt ein Abkühlen der Schmelze unter die Glasübergangstemperatur der Massivglas-bildenden Legierung unter Erhalt des Ingots (20). Bevorzugt wird die Schmelze bis auf Raumtemperatur abgekühlt. Die Abkühlgeschwindigkeit in Schritt c) ist erfindungsgemäß nicht weiter beschränkt. In einer möglichen Ausführungsform lässt man die Schmelze ohne zusätzliche Einwirkung (Heizen bzw. Kühlen) auf Raumtemperatur abkühlen. Alternativ kann die Schmelze aktiv unter die Glasübergangstemperatur abgekühlt werden, um den Prozess zu beschleunigen.In step c), the melt is cooled to below the glass transition temperature of the solid glass-forming alloy while retaining the ingot (20). The melt is preferably cooled down to room temperature. The cooling rate in step c) is not restricted further according to the invention. In one possible embodiment, the melt is allowed to cool to room temperature without additional action (heating or cooling). Alternatively, the melt can be actively cooled below the glass transition temperature in order to accelerate the process.
Durch das erfindungsgemäße Verfahren kann ein Ingot aus einer Massivglas-bildenden Legierung hergestellt werden, der nicht während des Herstellungsverfahrens zerspringt. Weiterhin kann durch das Verfahren ein Ingot hergestellt werden, der nicht zerspringt, wenn er innerhalb von maximal 50 Sekunden auf die Schmelztemperatur der Legierung erhitzt wird. Insbesondere kann ein Ingot hergestellt werden, der nicht zerspringt, wenn er drei Mal aus einer Höhe von 30 cm auf eine ebene, horizontale Stahloberfläche fällt. Insbesondere kann durch das Verfahren ein Ingot erzeugt werden, der an der Oberfläche keine amorphe Schicht aufweist. Die Abwesenheit einer amorphen Schicht kann im Lichtmikroskop bestimmt werden.With the method according to the invention, an ingot can be produced from an alloy which forms solid glass and which does not shatter during the production process. Furthermore, the method can be used to produce an ingot which does not crack if it is heated to the melting temperature of the alloy within a maximum of 50 seconds. In particular, an ingot can be produced that does not shatter if it falls three times from a height of 30 cm onto a flat, horizontal steel surface. In particular, the method can be used to produce an ingot which does not have an amorphous layer on the surface. The absence of an amorphous layer can be determined under a light microscope.
In einem weiteren Aspekt betrifft die Erfindung einen Ingot einer Massivglas-bildenden Legierung, wobei die Legierung eine kritischen Gussdicke von mindestens 5 mm aufweist, und wobei der Ingot in alle drei Raumrichtungen eine Ausdehnung aufweist, die größer ist als die kritische Gussdicke, dadurch gekennzeichnet, dass der Ingot, einen kristallinen Anteil von mindestens 90 Gew.-%, insbesondere mindestens 95 Gew.-% und besonders bevorzugt mindestens 98 Gew.-% aufweist, gemessen mittels DSC.In a further aspect, the invention relates to an ingot of a solid glass-forming alloy, wherein the alloy has a critical casting thickness of at least 5 mm, and wherein the ingot has an extension in all three spatial directions that is greater than the critical casting thickness, characterized in that that the ingot has a crystalline fraction of at least 90% by weight, in particular at least 95% by weight and particularly preferably at least 98% by weight, measured by means of DSC.
Bevorzugt beträgt die kritische Gussdicke der Legierung mindestens 7 mm und insbesondere mindestens 10 mm. Der erfindungsgemäße Ingot kann mithilfe des hierin beschriebenen Verfahrens hergestellt werden. In einer bevorzugten Ausführung weist der erfindungsgemäße Ingot keine amorphe Schicht auf der Oberfläche auf. Im Rahmen der vorliegenden Erfindung kann der Begriff "keine amorphe Schicht" verstanden werden als eine Schicht, die nicht dicker als 200 µm, insbesondere nicht dicker als 100 µm und ganz besonders bevorzugt nicht dicker als 50 µm ist. Die Abwesenheit einer amorphen Schicht kann bevorzugt zur Verringerung von Eigenspannungen im Ingot führen. Die Abwesenheit einer amorphen Schicht auf der Oberfläche des Ingots kann mittels optischer Mikroskopie (Auflicht-Mikroskop) bestimmt werden. Dazu wird mittels Diamantsäge ein Querschnitt des Ingots erzeugt. Der Querschnitt wird auch metallurgisches Schliffbild oder Querschliff genannt. Die Abwesenheit von amorphen Anteilen kann durch die Abwesenheit eines mit dem Auge sichtbaren Phasenübergangs im Lichtmikroskop bestimmt werden. Phasenübergänge können im Lichtmikroskop als Übergänge unterschiedlicher Farbe, bzw. unterschiedlichen Kontrasts identifiziert werden. In diesem Zusammenhang wird auf die Abbildungen 1 bis 3 verwiesen.
In einer Ausführungsform kann das gesamte Volumen der amorphen Schicht auf dem Ingot 5% oder weniger, insbesondere 3% oder weniger betragen. Die Kristallinität des Ingots kann mittels Differential Scanning Calorimetry (DSC) gemessen werden. Bevorzugt ist der Ingot massiv und weist keine Hohlräume, wie z.B. Lufteinschlüsse, auf. Erfindungsgemäß ist die Form des Ingots nicht beschränkt. In eine Ausführung kann der Ingot eine zylindrische Form aufweisen. Bevorzugt weist der Zylinderdurchmesser einen Wert von mindestens 5 mm, insbesondere mindestens 15 mm und ganz besonders bevorzugt mindestens 25 mm auf, jeweils unter der Bedingung, dass der Durchmesser größer ist als die kritische Gussdicke der Massivglas-bildenden Legierung. Die Länge des Zylinders beträgt bevorzugt mindestens 3 cm.In one embodiment, the total volume of the amorphous layer on the ingot can be 5% or less, in particular 3% or less. The crystallinity of the ingot can be measured using differential scanning calorimetry (DSC). The ingot is preferably solid and has no cavities, such as, for example, air pockets. According to the invention, the shape of the ingot is not limited. In one embodiment, the ingot can have a cylindrical shape. The cylinder diameter preferably has a value of at least 5 mm, in particular at least 15 mm and very particularly preferably at least 25 mm, in each case under the condition that the diameter is greater than the critical casting thickness of the solid glass-forming alloy. The length of the cylinder is preferably at least 3 cm.
In einem weiteren Aspekt betrifft die Erfindung ein Verfahren zur Herstellung von dreidimensionalen Bauteilen aus metallischen Massivgläsern mittels Gussverfahren, insbesondere Spritzguss, unter Verwendung des erfindungsgemäßen Ingots einer Massivglas-bildenden Legierung.In a further aspect, the invention relates to a method for producing three-dimensional components from solid metallic glasses by means of casting processes, in particular injection molding, using the inventive ingot of an alloy that forms solid glass.
Während der Herstellung des dreidimensionalen Bauteils mittels Gussverfahren, wie z.B. Spritzguss, wird der erfindungsgemäße Ingot zu einer homogenen Schmelze (30) geschmolzen. Bevorzugt dauert das vollständige Schmelzen des Ingots (20) nicht länger als 60 Sekunden, insbesondere nicht länger als 40 Sekunden und ganz besonders bevorzugt nicht länger als 20 Sekunden, wobei der Ingot erhitzt werden kann ohne zu zerspringen.During the production of the three-dimensional component by means of casting processes, e.g. Injection molding, the ingot according to the invention is melted into a homogeneous melt (30). The complete melting of the ingot (20) preferably takes no longer than 60 seconds, in particular no longer than 40 seconds, and very particularly preferably no longer than 20 seconds, with the ingot being able to be heated without cracking.
Herkömmliche Ingots können typischer Weise nur deutlich langsamer geschmolzen werden, da sie sonst zerspringen. Dies bringt die oben beschriebenen Nachteile mit sich. Die Aufheizdauer bei bereits bekannten Ingots gleicher Abmessung liegt typischer Weise im Bereich von 80 Sekunden. Nach dem Schmelzen des Ingots (20) wird die homogene Schmelze (30) in die Gussform für ein dreidimensionales Bauteil (40) gegossen, insbesondere gespritzt. Bevorzugt ist die Gussform zur Herstellung des dreidimensionalen Bauteils mittels Gussverfahren so dimensioniert, dass sie an keiner Stelle die kritische Gussdicke der verwendeten Legierung überschreitet, da so vollständig amorphe, dreidimensionale Bauteile erzeugt werden können. Insbesondere kann der Ingot zur Herstellung von dreidimensionalen Bauteilen verwendet werden, die mit einem hohen Durchsatz in einer Spritzgussmaschine hergestellt werden können.Conventional ingots can typically only be melted much more slowly, otherwise they will burst. This has the disadvantages described above. The heating time for already known ingots of the same size is typically in the range of 80 seconds. After the ingot (20) has melted, the homogeneous melt (30) is poured, in particular injected, into the casting mold for a three-dimensional component (40). The casting mold for producing the three-dimensional component by means of a casting process is preferably dimensioned such that it does not exceed the critical casting thickness of the alloy used at any point, since completely amorphous, three-dimensional components can be produced in this way. In particular, the ingot can be used to manufacture three-dimensional components that can be manufactured with a high throughput in an injection molding machine.
Die Durchführung der XRD - Messungen wird gemäß DIN EN 13925-1:2003-07 und DIN EN 13925-2:2003-07 durchgeführt. Mit einer Diamantsäge wird ein Querschliff des zu untersuchenden Materials angefertigt. Die plane Oberfläche des Querschliffs liegt im Bereich von ca. 1 cm2. Die allgemeine verwendeten Messdetails sind wie folgt zusammengefasst: Beugung: Bragg- Brentano; Detektor: Scintillation Counter; Strahlung: CuKα 1.5406 Å; Quelle: 40 kV, 25 mA; Messmethode: Reflektion.The XRD measurements are carried out in accordance with DIN EN 13925-1: 2003-07 and DIN EN 13925-2: 2003-07. A cross-section of the material to be examined is made with a diamond saw. The flat surface of the cross-section is in the region of approx. 1 cm 2 . The general measurement details used are summarized as follows: Diffraction: Bragg-Brentano; Detector: scintillation counter; Radiation: Cu Kα 1.5406 Å; Source: 40 kV, 25 mA; Measurement method: reflection.
Als interne Referenz wird zuerst der leere Probenhalter gemessen, um das Hintergrundsignal zu ermitteln. Diese Hintergrundmessung wird von allen folgenden Messungen der zu untersuchenden Proben abgezogen.As an internal reference, the empty sample holder is measured first to determine the background signal. This background measurement is subtracted from all subsequent measurements of the samples to be examined.
Diskrete Beugungssignale im Diffraktogramm, sofern vorhanden, können gemäß dem Debye-Scherrer Verfahren unter Verwendung der Bragg-Gleichung ausgewertet werden. Bei sichtbar werden von diskreten, kristallinen Peaks oberhalb des statistischen Rauschens geht man von einem kristallinen Anteil von mindestens 5 Gew.-% aus. Sind im Diffraktogramm keine scharfen Beugungssignale zu bestimmen, liegt der kristalline Anteil unter 5%.Discrete diffraction signals in the diffractogram, if any, can be evaluated according to the Debye-Scherrer method using the Bragg equation. When become visible from discrete, crystalline peaks above the statistical noise, a crystalline proportion of at least 5% by weight is assumed. If no sharp diffraction signals can be determined in the diffraction pattern, the crystalline portion is below 5%.
Die DSC-Messungen im Rahmen der Erfindung werden gemäß DIN EN ISO 11357-1:2017-02 und DIN EN ISO 11357-3:2018-07 durchgeführt. Die zu vermessende Probe in Form einer dünnen Scheibe oder Folie, (ca. 80 - 100 mg) wird in die Messvorrichtung (NETZSCH DSC 404F1, NETZSCH GmbH, Deutschland) gegeben. Die Aufheizrate beträgt 20,0 K/min. Als Tiegelmaterial wird Al2O3 verwendet. Die Messung des Wärmeflusses erfolgt gegenüber einem leeren Referenztiegel, sodass ausschließlich das thermische Verhalten der Probe gemessen wird.The DSC measurements within the scope of the invention are carried out in accordance with DIN EN ISO 11357-1: 2017-02 and DIN EN ISO 11357-3: 2018-07. The sample to be measured in the form of a thin disk or film (approx. 80-100 mg) is placed in the measuring device (NETZSCH DSC 404F1, NETZSCH GmbH, Germany). The heating rate is 20.0 K / min. Al 2 O 3 is used as the crucible material. The heat flow is measured against an empty reference crucible, so that only the thermal behavior of the sample is measured.
Das Messverfahren erfolgt gemäß den folgenden Schritten:
- a) Die zu vermessende Probe wird mit der oben genannten Aufheizrate auf eine Temperatur T kurz unterhalb der Schmelztemperatur aufgeheizt (T=0,75*Tm) und der Wärmefluss gemessen. Die Messung ist abgeschlossen, wenn kein Wärmefluss im Zusammenhang mit Phasenübergängen mehr gemessen werden kann. Insbesondere wird die Messung beendet, wenn ein exothermes Signal in Zusammenhang mit dem Kristallisationsvorgang vollständig erfasst ist. In den hierin enthaltenen Beispielen wird z.B. von Raumtemperatur bis etwa 600°C gemessen.
- b) Die Probe lässt man auf Raumtemperatur abkühlen.
- c) Die Probe wird erneut mit derselben Aufheizrate auf dieselbe Temperatur aufgeheizt wie in Schritt a) und der Wärmefluss wird gemessen.
- d) Die Messung aus Schritt c) wird von der Messung aus Schritt a) abgezogen, unter Erhalt der Messdifferenz. Aus der Differenzmessung wird die Kristallisationsenthalpie, falls vorhanden, durch Integralbildung bestimmt.
- a) The sample to be measured is heated to a temperature T just below the melting temperature (T = 0.75 * Tm) at the above-mentioned heating rate and the heat flow is measured. The measurement is completed when no more heat flow in connection with phase transitions can be measured. In particular, the measurement is ended when an exothermic signal in connection with the crystallization process is completely recorded. In the examples contained herein, for example, from room temperature to about 600 ° C. is measured.
- b) The sample is allowed to cool to room temperature.
- c) The sample is again heated to the same temperature at the same heating rate as in step a) and the heat flow is measured.
- d) The measurement from step c) is subtracted from the measurement from step a), while maintaining the measurement difference. The enthalpy of crystallization, if any, is determined from the difference measurement by forming an integral.
Proben, von denen erwartet wird, dass sie überwiegend kristallin sind und nur einen geringen Anteil an amorpher Phase aufweisen, werden gemäß der oben angegebenen Messmethode vermessen. Die Probe, z.B. aus einem erfindungsgemäßen Ingot, wird in Schritt a) bis auf eine Temperatur T = 0,75*Tm (75% der Schmelztemperatur (Tm) in °C) erhitzt. Wenn nach Abzug der Referenzmessung aus Schritt c) kein Wärmefluss im Bereich der Kristallisationstemperatur bestimmt werden kann, wird davon ausgegangen, dass die Probe vollständig kristallin ist (Messungenauigkeit 5%). Die vollständige Kristallinität der Probe nach dem Durchlaufen des Messverfahrens kann zusätzlich mittels XRD bestätigt werden, durch die Abwesenheit von breiten, unspezifischen Signalen im Beugungsdiagramm, die auf eine amorphe Phase hinweisen würden. Der amorphe Anteil von Proben mit mehr als 5 Gew.-% lässt sich durch Vergleich der Kristallisationsenthalpie der unbekannten Probe mit dem Wert für die vollständig amorphe Probe aus DSC-Verfahren 2) (s.u.) bestimmen.Samples that are expected to be predominantly crystalline and have only a small amount of amorphous phase are measured according to the measurement method given above. The sample, for example from an ingot according to the invention, is heated in step a) to a temperature T = 0.75 * Tm (75% of the melting temperature (Tm) in ° C.). If, after subtracting the reference measurement from step c), no heat flow can be determined in the range of the crystallization temperature, it is assumed that the sample is completely crystalline (
Für die Bestimmung der kritischen Gussdicke wird von jedem der gegossenen Zylinder eine Probe mittels DSC vermessen. Solang der Durchmesser der Zylinder unterhalb der kritischen Gussdicke liegt ist die Probe vor Beginn der Messung vollständig amorph und kristallisiert während der DSC-Messung in Schritt a) des Messverfahrens. Aus der Messung des vollständig amorphen Materials wird die Kristallisationsenthalpie der Legierung bestimmt. Die Kristallisationsenthalpie wird für alle Proben mit zunehmendem Zylinderdurchmesser bestimmt. Die bestimmte Kristallisationsenthalpie für Proben, deren Zylinderdurchmesser unterhalb der kritischen Gussdicke liegt, ist im Rahmen der Messungenauigkeit konstant. Sobald der Zylinderdurchmesser die kritische Gussdicke überschreitet, wird in der DSC-Messung der Probe für die Kristallisationsenthalpie ein kleinerer Wert gemessen als bei den kleineren Durchmessern, da bereits ein Teil des Materials kristallisiert ist und dies nichtmehr innerhalb der DSC-Messung geschieht. Die kritische Gussdicke wird als der Zylinderdurchmesser bestimmt, bis zu dem die Kristallisationsenthalpie bei aufsteigendem Durchmesser konstant ist.To determine the critical casting thickness, a sample of each of the cast cylinders is measured using DSC. As long as the diameter of the cylinder is below the critical casting thickness, the sample is completely amorphous before the start of the measurement and crystallizes during the DSC measurement in step a) of the measurement process. The enthalpy of crystallization of the alloy is determined from the measurement of the completely amorphous material. The enthalpy of crystallization is determined for all samples with increasing cylinder diameter. The specific enthalpy of crystallization for samples whose cylinder diameter is below the critical casting thickness is constant within the scope of the measurement inaccuracy. As soon as the cylinder diameter exceeds the critical casting thickness, a smaller value is measured for the enthalpy of crystallization in the DSC measurement of the sample than for the smaller diameters, as part of the material has already crystallized and this no longer happens within the DSC measurement. The critical casting thickness is determined as the cylinder diameter up to which the enthalpy of crystallization is constant with increasing diameter.
Im Rahmen der vorliegenden Erfindung wird die Glasübergangstemperatur gemäß ASTM E1365-03 wie folgt gemessen. Die zu untersuchende Probe wird in einem DSC-Gerät (NETZSCH DSC 404F1, NETZSCH GmbH, Deutschland) in einen Tiegel gegeben. Das System wird nach dem folgenden Schema geheizt und gekühlt und der jeweilige Wärmefluss in den Schritten a) und c) gemessen.
- a) Erwärmen auf eine Temperatur von 0,75*Tm mit einer Heizrate von 20K/min.
- b) Abkühlen auf Raumtemperatur
- c) Erwärmen auf die gleiche Temperatur wie in Schritt a) mit der gleichen Heizrate, und
- d) Abkühlen auf Raumtemperatur.
- a) Heating to a temperature of 0.75 * Tm with a heating rate of 20K / min.
- b) cooling to room temperature
- c) heating to the same temperature as in step a) with the same heating rate, and
- d) cooling to room temperature.
Als Resultat des Experiments wird die Enthalpie in Abhängigkeit von der Temperatur für die Probe erhalten. In Schritt a) findet die Kristallisation der amorphen Probe statt. In Schritt c) wird das thermische Verhalten der bereits vollständig kristallisierten Probe aufgezeichnet.As a result of the experiment, the enthalpy is obtained as a function of the temperature for the sample. In step a) the amorphous sample is crystallized. In step c) the thermal behavior of the already completely crystallized sample is recorded.
Um die Glasübergangstemperatur zu bestimmen, wird die Messung aus Schritt c) von der Messung aus Schritt a) subtrahiert. Die resultierende Kurve beinhaltet einen endothermen Übergang bei niedrigere Temperatur und ein exothermes Signal bei höherer Temperatur. Das Signal bei höherer Temperatur korrespondiert mit dem Kristallisationsvorgang. Das endotherme Signal korrespondiert mit dem Glasübergang. Um die Glasübergangstemperatur zu bestimmen, wird vor dem Glasübergangsbereich eine Tangentenlinie zur Basislinie bestimmt (durch lineare Anpassung). Eine zweite Tangente wird im Wendepunkt (entsprechend dem zeitlichen Spitzenwert der ersten Ableitung) des Glasübergangsbereichs bestimmt. Der Temperaturwert am Schnittpunkt der beiden Tangenten gibt die Glasübergangstemperatur an (Tf gemäß AST; 1356-03).In order to determine the glass transition temperature, the measurement from step c) is subtracted from the measurement from step a). The resulting curve includes an endothermic transition at a lower temperature and an exothermic signal at a higher temperature. The signal at a higher temperature corresponds to the crystallization process. The endothermic signal corresponds to the glass transition. To determine the glass transition temperature, a tangent line to the baseline is determined in front of the glass transition area (by linear fitting). A second tangent is determined at the point of inflection (corresponding to the peak value of the first derivative over time) of the glass transition region. The temperature value at the intersection of the two tangents indicates the glass transition temperature (T f according to AST; 1356-03).
Die einzelnen Komponenten wurde unter Schutzgas mittels induktivem Schmelzen zu einer homogenen Legierung der Zusammensetzung Zr52,5Ti5Cu17,9Ni14,6Al10 geschmolzen. Diese Legierung weist eine Glasübergangstemperatur von 403 °C auf. 80 g der homogenen Legierung wurden mittels induktivem Heizen in einem Schmelztiegel auf eine Temperatur oberhalb der Schmelztemperatur der Legierung (805°C) gebracht. Die Temperaturen der jeweiligen Schmelze für den jeweiligen Versuch sind Tabelle 1 zu entnehmen. Die Gussform wurde jeweils in einem Ofen auf eine in Tabelle 1 definierte Temperatur vorgeheizt. Anschließend wurde die jeweilige homogene Schmelze gemäß Tabelle 1 in eine Gussform gefüllt. Die Gussform hatte eine zylindrische Form mit einem Innendurchmesser von 19 mm. Die Temperatur der Schmelze wurde nach dem Füllen der zylindrischen Gussform kontinuierlich gemessen. Die Messwerte für die Temperatur der Schmelze nach 10 Sekunden in der Gussform sind jeweils in Tabelle 1 abzulesen.
Beispiele 1 und 2 in Tabelle 1 sind Vergleichsbeispiele, Beispiele 3-5 sind erfindungsgemäße Beispiele. Die Beurteilung der Qualität der gegossenen Ingots erfolgte nach den folgenden Kriterien: Gegossene Teile mit schlechter Qualität zerspringen bereits während des Erkaltens in der Gussform. Gegossene Ingots mit guter Qualität bleiben intakt, wenn sie innerhalb von höchstens 50 Sekunden mit einer Leistung von 5 kW auf die Schmelztemperatur erhitzt wurden. Ingots mit sehr guter Qualität überstehen zusätzlich einen Fall-Test aus 30 cm Höhe auf eine ebene Stahlplatte dreimal hintereinander, ohne zu zerspringen. Aus den Beispielen 1-5 wird deutlich, dass Ingots, bei denen die Temperatur der Schmelze nach 10 Sekunden über der Glasübergangstemperatur lag, deutlich robuster waren als Ingots bei denen die Temperatur der Schmelze darunter lag.Examples 1 and 2 in Table 1 are comparative examples, Examples 3-5 are examples according to the invention. The quality of the cast ingots was assessed according to the following criteria: Cast parts of poor quality shatter as soon as they cool in the mold. Good quality cast ingots remain intact if they are heated to the melting temperature within 50 seconds or less with an output of 5 kW. Very good quality ingots also withstand a drop test from a height of 30 cm onto a flat steel plate three times in a row without cracking. It is clear from Examples 1-5 that ingots in which the temperature of the melt was above the glass transition temperature after 10 seconds were significantly more robust than ingots in which the temperature of the melt was below.
Beschreibung der Abbildungen:
-
zeigt eine Aufnahme mit dem Lichtmikroskop, die den Querschnitt eines Ingots zeigt, der gemäß Beispiel 1 als Vergleichsversuch gefertigt wurde. Die hellen Bereiche im Querschnitt, die beispielhaft mit Pfeilen gekennzeichnet sind, zeigen amorphe Bereiche (Pfeil 1), die von dunkleren, kristallinen Bereichen umgeben sind (Pfeil 2). Weiterhin ist inAbbildung 1 zu erkennen, dass der Ingot gesprungen ist.Abbildung 1 -
zeigt eine Aufnahme mit dem Lichtmikroskop, die den Querschnitts eines Ingots zeigt, der gemäß Beispiel 4 gefertigt wurde. Der Querschnitt eines Ingots gemäßAbbildung 2Beispiel 4 zeigt eine homogene Materialverteilung ohne helle Bereiche, die auf amorphe Phasen hindeuten würden. -
zeigt eine Vergrößerung der erfindungsgemäßenAbbildung 3Probe aus Abbildung 2 . Das Bild zeigt die multikristalline Struktur des Ingots bis in den Randbereich des Querschnitts. -
zeigt eine schematische Darstellung des Verfahrensverlaufs von den Einzelkomponenten der Massivglas-bildendenden Legierung (5) bis zum Bauteil aus metallischem Massivglas (40). Dabei werden die folgenden Stufen durchlaufen: Einzelkomponenten der Massivglas-bildendenden Legierung (5), homogene Schmelze (10), Ingot aus Massivglas-bildender Legierung (20), homogene Schmelze der Massivglas-bildenden Legierung (30) und Bauteil aus metallischem Massivglas (40).Abbildung 4
-
illustration 1illustration 1 -
Figure 2 FIG. 13 shows a photo taken with the light microscope showing the cross section of an ingot which was manufactured according to Example 4. The cross section of an ingot according to Example 4 shows a homogeneous material distribution without light areas which would indicate amorphous phases. -
Figure 3 shows an enlargement of the sample according to the inventionFigure 2 . The picture shows the multicrystalline structure of the ingot up to the edge of the cross-section. -
Figure 4 shows a schematic representation of the course of the process from the individual components of the solid glass-forming alloy (5) to the component made of metallic solid glass (40). The following stages are run through: Individual components of the solid glass-forming alloy (5), homogeneous melt (10), ingot made of solid glass-forming alloy (20), homogeneous melt of the solid glass-forming alloy (30) and component made of metallic solid glass (40 ).
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PCT/EP2020/052232 WO2020164916A1 (en) | 2019-02-13 | 2020-01-30 | Robust ingot for the production of components made of metallic solid glasses |
US17/427,597 US20220118511A1 (en) | 2019-02-13 | 2020-01-30 | Robust ingot for the production of components made of metallic solid glasses |
CN202080011844.XA CN113382815B (en) | 2019-02-13 | 2020-01-30 | Stable ingots for producing components made of bulk metallic glass |
TW109103520A TWI791947B (en) | 2019-02-13 | 2020-02-05 | Robust ingot for production of components made of bulk metallic glasses |
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DE10326769B3 (en) * | 2003-06-13 | 2004-11-11 | Esk Ceramics Gmbh & Co. Kg | Slip for producing long-lasting mold release layer, useful on mold for casting nonferrous metal under pressure, comprises boron nitride suspension in silanized silica in organic solvent or aqueous colloidal zirconia, alumina or boehmite |
US9790580B1 (en) * | 2013-11-18 | 2017-10-17 | Materion Corporation | Methods for making bulk metallic glasses containing metalloids |
US9802247B1 (en) * | 2013-02-15 | 2017-10-31 | Materion Corporation | Systems and methods for counter gravity casting for bulk amorphous alloys |
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CN1438083A (en) * | 2003-03-07 | 2003-08-27 | 江苏大学 | Method for making block metal glass using quick-cooling technology |
CN100398687C (en) * | 2005-08-31 | 2008-07-02 | 中国科学院物理研究所 | Samarium based amorphous alloy and preparation method thereof |
EP2113759A1 (en) * | 2008-04-29 | 2009-11-04 | The Swatch Group Research and Development Ltd. | Pressure sensor having a membrane comprising an amorphous material |
US8887532B2 (en) * | 2010-08-24 | 2014-11-18 | Corning Incorporated | Glass-forming tools and methods |
CN104213054B (en) * | 2014-09-03 | 2017-02-15 | 中国科学院金属研究所 | Liquid-phase separation biphasic bulk metallic glass material and preparation method thereof |
JP6334626B2 (en) * | 2016-09-01 | 2018-05-30 | アップル インコーポレイテッド | Continuous production of amorphous alloy ingot without mold |
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US5279349A (en) | 1989-12-29 | 1994-01-18 | Honda Giken Kogyo Kabushiki Kaisha | Process for casting amorphous alloy member |
DE10326769B3 (en) * | 2003-06-13 | 2004-11-11 | Esk Ceramics Gmbh & Co. Kg | Slip for producing long-lasting mold release layer, useful on mold for casting nonferrous metal under pressure, comprises boron nitride suspension in silanized silica in organic solvent or aqueous colloidal zirconia, alumina or boehmite |
US9802247B1 (en) * | 2013-02-15 | 2017-10-31 | Materion Corporation | Systems and methods for counter gravity casting for bulk amorphous alloys |
US9790580B1 (en) * | 2013-11-18 | 2017-10-17 | Materion Corporation | Methods for making bulk metallic glasses containing metalloids |
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US20220098714A1 (en) * | 2020-09-28 | 2022-03-31 | Seoul National University R&Db Foundation | Resettable gears and manufacturing method therefor |
US11873548B2 (en) * | 2020-09-28 | 2024-01-16 | Seoul National University R&Db Foundation | Resettable gears and manufacturing method therefor |
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