EP1545812B1 - Casting of non-ferrous metals - Google Patents
Casting of non-ferrous metals Download PDFInfo
- Publication number
- EP1545812B1 EP1545812B1 EP03737080.6A EP03737080A EP1545812B1 EP 1545812 B1 EP1545812 B1 EP 1545812B1 EP 03737080 A EP03737080 A EP 03737080A EP 1545812 B1 EP1545812 B1 EP 1545812B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- metal
- casting
- product
- nip
- strip
- 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.)
- Expired - Lifetime
Links
- 229910052751 metal Inorganic materials 0.000 title claims description 139
- 239000002184 metal Substances 0.000 title claims description 139
- 238000005266 casting Methods 0.000 title claims description 121
- -1 ferrous metals Chemical class 0.000 title description 2
- 239000007787 solid Substances 0.000 claims description 42
- 238000000034 method Methods 0.000 claims description 41
- 210000001787 dendrite Anatomy 0.000 claims description 36
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 11
- 229910000861 Mg alloy Inorganic materials 0.000 claims description 10
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 claims description 8
- 239000010936 titanium Substances 0.000 claims description 8
- 229910001069 Ti alloy Inorganic materials 0.000 claims description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 6
- 239000010949 copper Substances 0.000 claims description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 5
- 239000011701 zinc Substances 0.000 claims description 5
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 4
- 239000011135 tin Substances 0.000 claims description 4
- 229910000881 Cu alloy Inorganic materials 0.000 claims description 2
- 229910000990 Ni alloy Inorganic materials 0.000 claims description 2
- 229910001128 Sn alloy Inorganic materials 0.000 claims description 2
- 229910001297 Zn alloy Inorganic materials 0.000 claims description 2
- 239000000047 product Substances 0.000 description 47
- 229910000838 Al alloy Inorganic materials 0.000 description 22
- 229910021652 non-ferrous alloy Inorganic materials 0.000 description 21
- 229910045601 alloy Inorganic materials 0.000 description 17
- 239000000956 alloy Substances 0.000 description 17
- 238000007711 solidification Methods 0.000 description 15
- 230000008023 solidification Effects 0.000 description 15
- 238000012546 transfer Methods 0.000 description 14
- 238000011144 upstream manufacturing Methods 0.000 description 14
- 238000004519 manufacturing process Methods 0.000 description 12
- 238000001816 cooling Methods 0.000 description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 9
- 238000005204 segregation Methods 0.000 description 9
- 238000005275 alloying Methods 0.000 description 8
- 230000008569 process Effects 0.000 description 8
- 230000002829 reductive effect Effects 0.000 description 8
- 238000005096 rolling process Methods 0.000 description 8
- 229910000831 Steel Inorganic materials 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 239000010959 steel Substances 0.000 description 7
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 6
- 230000005496 eutectics Effects 0.000 description 6
- 239000011777 magnesium Substances 0.000 description 6
- 230000007246 mechanism Effects 0.000 description 6
- 230000009467 reduction Effects 0.000 description 6
- 238000009749 continuous casting Methods 0.000 description 5
- 230000003247 decreasing effect Effects 0.000 description 4
- 229910052749 magnesium Inorganic materials 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 230000003647 oxidation Effects 0.000 description 4
- 238000007254 oxidation reaction Methods 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000001125 extrusion Methods 0.000 description 3
- 230000000670 limiting effect Effects 0.000 description 3
- 238000003756 stirring Methods 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- 238000010923 batch production Methods 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000001680 brushing effect Effects 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 239000011888 foil Substances 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 229910001092 metal group alloy Inorganic materials 0.000 description 2
- 239000004033 plastic Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 230000002441 reversible effect Effects 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 229910052718 tin Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018137 Al-Zn Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 229910018573 Al—Zn Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 241000490229 Eucephalus Species 0.000 description 1
- 235000015842 Hesperis Nutrition 0.000 description 1
- 235000012633 Iberis amara Nutrition 0.000 description 1
- 229910003023 Mg-Al Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- SNAAJJQQZSMGQD-UHFFFAOYSA-N aluminum magnesium Chemical compound [Mg].[Al] SNAAJJQQZSMGQD-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 235000013361 beverage Nutrition 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000007795 chemical reaction product Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000001010 compromised effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000011152 fibreglass Substances 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 238000010907 mechanical stirring Methods 0.000 description 1
- 238000005058 metal casting Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000003607 modifier Substances 0.000 description 1
- 239000004570 mortar (masonry) Substances 0.000 description 1
- 239000010813 municipal solid waste Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 239000004753 textile Substances 0.000 description 1
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0605—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two belts, e.g. Hazelett-process
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/10—Supplying or treating molten metal
Definitions
- the present invention relates to casting of non-ferrous metal alloys, more particularly, to casting non-ferrous metal alloys to create a rapidly solidified shell or shells and a segregation-free center zone containing broken dendrites.
- Twin roll casting traditionally is a combined solidification and deformation technique involving feeding molten metal into the bite between a pair of counter-rotating cooled rolls wherein solidification is initiated when the molten metal contacts the rolls.
- Solidified metal forms as a "freeze front" of the molten metal within the roll bite and solid metal' advances towards the nip, the point of minimum clearance between the rolls.
- the solid metal passes through the nip as a solid sheet. The solid sheet is deformed by the rolls (hot rolled) and exits the rolls.
- Aluminum alloys have successfully been roll cast into 0.63 cm (1 ⁇ 4inch) thick sheet at at about 1-22 - 1.83 m/min (4-6 feet per minute) or about 0.89 - 1.25 kg per hour per cm of cas width (50-70 pounds per hour per inch of cast width (lbs/hr/in)). Attempts to increase the speed of roll casting typically fail due to centerline segregation. Although it is generally accepted that reduced gauge sheet (e.g., less than about 0.63 cm (1 ⁇ 4 inch) thick) potentially could be produced more quickly than higher gauge sheet in a roll caster, the ability to roll cast aluminum at rates significantly above about 1.25 kg/hr/cm (70 lbs/hr/in) has been elusive.
- a molten metal holding chamber H is connected to a feed tip T which distributes molten metal M between water-cooled twin rolls R 1 and R 2 rotating in the direction of the arrows A 1 and A 2 , respectively.
- the rolls R 1 and R 2 have respective smooth surfaces U 1 and U 2 ; any roughness thereon is an artifact of the roll grinding technique employed during their manufacture.
- the centerlines of the rolls R 1 and R 2 are in a vertical or generally vertical plane L (e.g., up to about 15° from vertical) such that the cast strip S forms in a generally horizontal path.
- the width of the cast strip S is determined by the width of the tip T.
- the plane L passes through a region of minimum clearance between the rolls R 1 and R 2 referred to as the roll nip N.
- a solidification region exists between the solid cast strip S and the molten metal M and includes a mixed liquid-solid phase region X.
- a freeze front F is defined between the region X and the cast strip S as a line of complete solidification.
- the heat of the molten metal M is transferred to the rolls R 1 and R 2 such that the location of the freeze front F is maintained upstream of the nip N. In this manner, the molten metal M solidifies at a thickness greater than the dimension of the nip N.
- the solid cast strip S is deformed by the rolls R 1 and R 2 to achieve the final strip thickness. Hot rolling of the solidified strip between the rolls R 1 and R 2 according to conventional roll casting produces unique properties in the strip characteristic of roll cast aluminum alloy strip.
- a central zone through the thickness of the strip becomes enriched in eutectic forming elements (eutectic formers) in the alloy such as Fe, Si, Ni, Zn and the like and depleted in peritectic forming elements (Ti, Cr, V and Zr).
- eutectic formers i.e., alloying elements other than Ti, Cr, V and Zr
- This enrichment of eutectic formers (i.e., alloying elements other than Ti, Cr, V and Zr) in the central zone occurs because that portion of the strip S corresponds to a region of the freeze front F where solidification occurs last and is known as "centerline segregation". Extensive centerline segregation in the as-cast strip is a factor that restricts the speed of conventional roll casters.
- the as-cast strip also shows signs of working by the rolls. Grains which form during solidification of the metal upstream of the nip become flattened by the rolls. Therefore, roll cast aluminum includes grains elongated at
- the roll gap at the nip N may be reduced in order to produce thinner gauge strip S.
- the roll separating force generated by the solid metal between the rolls R 1 and R 2 increases.
- the amount of roll separating force is affected by the location of the freeze front F in relation to the roll nip N.
- the roll gap is reduced, the percentage reduction of the metal sheet is increased, and the roll separating force increases.
- the relative positions of the rolls R 1 and R 2 to achieve the desired roll gap cannot overcome the roll separating force, and the minimum gauge thickness has been reached for that position of the freeze front F.
- the roll separating force may be reduced by increasing the speed of the rolls in order to move the freeze front F downstream towards the nip N.
- the roll gap may be reduced.
- This movement of the freeze front F decreases the ratio between the thickness of the strip at the initial point of solidification and the roll gap at the nip N, thus decreasing the roll separating force as proportionally less solidified metal is being compressed and hot rolled. In this manner, as the position of the freeze front F moves toward the nip N, a proportionally greater amount of metal is solidified and then hot rolled at thinner gauges.
- roll casting of thin gauge strip is accomplished by first roll casting a relatively high gauge strip, decreasing the gauge until a maximum roll separating force is reached, advancing the freeze front to lower the roll separating force (by increasing the roll speed) and further decreasing the gauge until the maximum roll separating force is again reached, and repeating the process of advancing the freeze front and decreasing the gauge in an iterative manner until the desired thin gauge is achieved.
- a 10 millimeter strip S may be rolled and the thickness may be reduced until the roll separating force becomes excessive (e.g., at 6 millimeters), necessitating a roll speed increase.
- a major impediment to high-speed roll casting is the difficulty in achieving uniform heat transfer from the molten metal to the smooth surfaces U 1 and U 2 , i.e., cooling of the molten metal.
- the surfaces U 1 and U 2 include various imperfections which alter the heat transfer properties of the rolls.
- such non-uniformity in heat transfer becomes problematic. For example, areas of the surfaces U 1 and U 2 with proper heat transfer will cool the molten metal M at the desired location upstream of the nip N whereas areas with insufficient heat transfer properties will allow a portion of the molten metal to advance beyond the desired location and create non-uniformity in the cast strip.
- Thin gauge steel strip has been successfully roll cast in vertical casters at high speeds (up to about 122 m/min (400 feet per minute)) and low roll separating forces.
- the rolls of a vertical roll caster are positioned side by side so that the strip forms in a downward direction. In this vertical orientation, molten steel is delivered to the bite between the rolls to form a pool of molten steel.
- the upper surface of the pool of molten steel is often protected from the atmosphere by means of an inert gas.
- the casting belts converge directly opposite each other around the upstream rollers to form an entrance to the casting region in the nip between the upstream rollers.
- the molten metal is fed directly into the nip.
- the molten metal is confined between the moving belts and is solidified as it is carried along. Heat liberated by the solidifying metal is withdrawn through the portions of the two belts which are adjacent to the metal being cast This heat is withdrawn by cooling the reverse surfaces of the belts by means of rapidly moving substantially continuous films of water flowing against and communicating with these reverse surfaces.
- the operating parameters for belt casting are significantly different from those for roll casting.
- Solidification of the metal is completed in a distance of about 12-15 inches (30-38 mm) downstream of the nip for a thickness of 1.89 cm (3 ⁇ 4 inch).
- the belts are exposed to high temperatures when contacted by molten metal on one surface and are cooled by water on the inner surface. This may lead to distortion of the belts.
- the tension in the belt must be adjusted to account for expansion or contraction of the belt due to temperature fluctuations in order to achieve consistent surface quality of the strip.
- Casting of aluminum alloys on a belt caster has been used to d ate mainly for products having minimal surface quality requirements or for products which are subsequently painted.
- Block casters include a plurality of chilling blocks mounted adjacent to each other on a pair of opposing tracks. Each set of chilling blocks rotates in the opposite direction to form a casting region therebetween into which molten metal is delivered.
- the chilling blocks act as heat sinks as the heat of the molten metal transfers thereto. Solidification of the metal is complete about 30 - 37.5 cm (12-15 inches) downstream of the entrance to the casting region at a thickness of 1.875 cm (3 ⁇ 4 inch).
- the heat transferred to the chilling blocks is removed during the return loop.
- the shilling blocks are not functionally distorted by the heat transfer.
- block casters require precise dimensional control to prevent gaps between the blocks which cause non-uniformity and defects in the cast strip.
- the heat of the molten metal and the cast strip is transferred to the belts within the casting region (including downstream of the nip).
- the heat is then removed from the belts while the belts are out of contact with either of the molten metal or the cast strip.
- the portions of the belts within the casting region (in contact with the molten metal and cast strip) are not subjected to large variations in temperature as occurs in conventional belt casters.
- the thickness of the strip can be limited by the heat capacity of the belts between which casting takes place. Production rates of 429 kg/hr/cm (2400 lbs/hr/in) for 0.08-0.1 inch (2-2.5 mm) strip have been achieved.
- Strip material of non-ferrous alloys are desirable for use as sheet product in the automotive and aerospace industries and in the production of can bodies and can end and tab stock.
- Conventional manufacturing of can body stock employs batch processes which include an extensive sequence of separate steps. When an ingot i s needed for further processing, it is first scalped, heat treated to homogenize the alloy, cooled and rolled while still hot in a number of passes, hot finish rolled, and finally coiled, air cooled and stored. The coil may be annealed in a batch step. The coiled sheet stock is then further reduced to final gauge by cold rolling using unwinders, rewinders and single and/or tandem rolling mills.
- These batch processes typically used in the aluminum industry require many different material handling operations to move ingots and coils between what are typically separate processing steps.
- U. S. Patent Nos. 5,772 , 802 and 5,772 , 799 disclose belt casting methods in which can or lid stock and a method for its manufacture in which a low alloy content aluminum alloy is strip cast to form a hot strip cast feedstock, the hot feedstock is rapidly quenched to prevent substantial precipitation, annealed and quenched rapidly to prevent substantial precipitation of alloying elements and then cold rolled. This process has been successful despite the relatively low production rates achievable to date.
- US-2,693,012 discloses a process for fabricating sheet stock from molten metal.
- Molten metal is fed continuously to the bight of a pair of cooled rolls driven at high rotation speed to produce a sheet with thickness 1.65 mm.
- a retaining skin of metal adjacent to the roll is formed and a plastic condition in the central portion of the remaining metal is created.
- the plastic metal is mechanically worked and finally frozen completely immediately before the instant the sheet metal passes through the bight of the rolls.
- magnesium metal has a hexagonal crystal structure that severely restricts the amount of deformation that can be applied, particularly at low temperatures.
- Production of wrought magnesium alloy products is therefore normally carried out by hot working in the range of 300 -500 C. Even under those conditions, a multitude of rolling passes and intermediate anneals are needed. In the conventional ingot method, a total of up to 25 rolling passes with intermediate anneals are used to make a finished product of 0.5 mm gauge. As a result, magnesium wrought products tend to be expensive.
- a method of continuously casting molten metal into a metal product comprising the steps of:
- the metal is an alloy of magnesium or titanium.
- the product exits the nip at least 30.5 metres per minute (100 feet per minute).
- the thickness of the solidified inner layer comprises 20% to 30% of thickness of the product.
- the casting surfaces are textured to provide surface irregularities which contact the molten metal.
- said surface irregularities are in the form of grooves, dimples or knurls.
- said surface irregularities are spaced apart in a regular pattern of 20 to 120 irregularities per inch (8 to 48 irregularities per cm.)
- said surface irregularities are spaced apart in a regular pattern of 60 irregularities per inch (24 irregularities per cm.)
- said surface irregularities have a height of 5 to 50 micrometres.
- said surface irregularities have a height of 30 micrometres.
- the casting surfaces are continuously brushed in regions remote from the product to remove debris which might build up.
- Fig. 1 is a schematic of a portion of a caster with a molten metal delivery tip and a pair of rolls;
- Fig. 2 is an enlarged cross-sectioned schematic of the molten metal delivery tip and rolls shown in Fig. 1 operated according to the prior art;
- Fig. 3 is flow chart of steps of the casting method of the present invention.
- Fig.4 is a schematic of molten metal casting operated according to the present invention
- Fig. 5 is a schematic of a caster made in accordance with the present invention with a strip support mechanism and optional cooling means;
- Fig. 6 is a schematic of a caster made in accordance with the present invention with another strip support mechanism and optional cooling means.
- the present invention includes a method of casting non-ferrous alloy which includes delivering molten non-ferrous alloy to a casting apparatus.
- non-ferrous alloy it is meant an alloy of an element such as magnesium, titanium, copper, nickel, zinc or tin.
- Particularly suitable non-ferrous alloys for use in the present invention are magnesium alloys and titanium alloys.
- magnesium alloys and “titanium alloys” are intended to mean alloys containing at least 50 wt% of the stated element and at least one modifier element. Magnesium, and titanium alloys are considered attractive candidates for structural use in aerospace and automotive industries because of their light weight, high strength to weight ratio, and high specific stiffness at both room and elevated temperatures.
- systems of magnesium based alloys are Mg-Al system; Mg-Al-Zn system; Mg-Al-Si system; Mg-Al-Rare Earth (RE) system; Mg-Th-Zr system; Mg-Th-Zn-Zr system; Mg-Zn-Zr system; and Mg-Zn-Zr-RE system.
- step 100 molten non-ferrous metal is delivered to a casting apparatus.
- the casting apparatus includes a pair of spaced apart advancing casting surfaces such as described in detail below.
- step 102 the casting apparatus rapidly cools at least a portion of the non-ferrous alloy to solidify an outer layer of the non-ferrous alloy while maintaining a semi-solid inner layer.
- the inner layer includes a molten metal component and a solid component of dendrites of the metal.
- the solidified outer layer increases in thickness as the alloy is cast.
- the dendrites of the inner layer are altered in step 104, such as by breaking the dendrites into smaller structures.
- step 106 the inner layer is solidified.
- the product exiting the casting apparatus includes the solid inner layer formed in step 106 containing the broken dendrites sandwiched, within the outer solid layer of alloy.
- the product may bein various forms such as but not limited to sheet, plate, slab, and foil.
- the product may be in the form of a wire, rod, bar or other extrusion. In either case, the product may be further processed and/or treated in step 108.
- the order of steps 100-108 are not fixed in the method of the present invention and may occur sequentially or some of the steps may occur simultaneously.
- the present invention balances the rate of solidification of the molten metal, the formation of dendrites in the solidifying metal and alteration of the dendrites to obtain desired properties in the final product.
- the cooling rate is selected. to achieve rapid solidification of the outer layers of the metal.
- cooling of the outer layers of metal may occur at a rate of at least about 100° C per minute.
- Suitable casting apparatuses include cooled casting surfaces such as in a twin roll caster, a belt caster, a slab caster, or a block caster. Vertical roll casters may also be used in the present invention. In a continuous caster, the casting surfaces generally are spaced apart and have a region at which the distance therebetween is at a minimum.
- the region of minimum distance between casting surfaces is the nip.
- the region of minimum distance between casting surfaces of the belts may be the nip between the entrance pulleys of the caster.
- operation of a casting apparatus in the regime of the present invention involves solidification of the metal at the location of a minimum distance between the casting surfaces. While the method of present invention is described below as performed using a twin roll caster, this is not meant to be limiting. Other continuous casting surfaces may be used to practice the invention.
- a roll caster ( Fig. 1 ) may be operated to practice the present invention as shown in detail in Fig. 4 .
- Fig. 1 which generically depicts horizontal continuous casting according to the prior art and according to the present invention
- the present invention is practiced using a pair of counter-rotating cooled rolls R 1 and R 2 rotating in the directions of the arrows A 1 and A 2 , respectively.
- horizontal it is meant that the cast strip is produced in a horizontal orientation or at an angle of plus or minus about 30° from horizontal.
- Fig. 1 which generically depicts horizontal continuous casting according to the prior art and according to the present invention
- a feed tip T which may be made from a refractory or other ceramic material, distributes molten metal M in the direction of arrow B directly onto the rolls R 1 and R 2 rotating in the direction of the arrows A 1 and A 2 , respectively.
- Gaps G 1 and G 2 between the feed tip T and the respective rolls R 1 and R 2 are maintained as small as possible to prevent molten metal from leaking out and to minimize the exposure of the molten metal to the atmosphere along the rolls R 1 and R 2 yet avoid contact between the tip T and the rolls R 1 and R 2 .
- a suitable dimension of the gaps G 1 and G 2 is about 0.01 inch (0.25 mm).
- a plane L through the centerline of the rolls R 1 and R 2 passes through a region of minimum clearance between the rolls R 1 and R 2 referred to as the roll nip N.
- Molten metal M is provided to the casting surfaces of the roll caster, the cooled rolls R 1 and R 2 .
- the molten metal M directly contacts the rolls R 1 and R 2 at regions 2 and 4, respectively.
- the metal M Upon contact with the rolls R 1 and R 2 , the metal M begins to cool and solidify.
- the cooling metal solidifies as an upper shell 6 of solidified metal adjacent the roll R 1 and a lower shell 8 of solidified metal adjacent to the roll R 2 .
- the thickness of the shells 6 and 8 increases as the metal M advances towards the nip N. Large dendrites 10 of solidified metal (not shown to scale) are produced at the interfaces between each of the upper and lower shells 6 and 8 and the molten metal M.
- the large dendrites 10 are broken and dragged into a center portion 12 of the slower moving flow of the molten metal M and are carried in the direction of arrows C 1 and C 2 .
- the dragging action of the flow can cause the large dendrites 10 to be broken further into smaller dendrites 14 (not shown to scale).
- the metal M is semi-solid and includes a solid component (the solidified small dendrites 14) and a molten metal component.
- the metal M in the region 16 has a mushy consistency due in part to the dispersion of the small dendrites 14 therein.
- the central portion 12 is a solid central layer 18 containing the small dendrites 14 sandwiched between the upper shell 6 and the lower shell 8.
- the small dendrites 14 may be about 20 to about 50 microns in size and have a generally globular shape.
- the solid inner portion may constitute about 20 to about 30 percent of the total thickness of the strip. While the caster of Fig. 4 is shown as producing strip S in a generally horizontal orientation, this is not meant to be limiting as the strip S may exit the caster at an angle or vertically.
- the casting process described in relation to Fig. 4 follows the method steps outlined above.
- Molten metal delivered in step 100 to the roll caster begins to cool and solidify in step 102.
- the cooling metal develops outer layers of solidified metal 6 and 8 near or adjacent the cooled casting surfaces (R 1 and R 2 ).
- the thickness of the solidified layers 6 and 8 increases as the metal advances through the casting apparatus.
- dendrites 10 form in the metal in an inner layer 12 that is at least partially surrounded by the solidified outer layers 6 and 8.
- the outer layers 6 and 8 substantially surround the inner layer 12 as a sandwich of the inner layer 12 between the two outer layers 6 and 8. In other casting apparatuses the outer layer may completely surround the inner layer.
- the dendrites 10 are altered, e.g., broken into smaller structures 14.
- the metal is semi-solid and includes a solid component (the solidified small dendrites 14) and a molten metal component.
- the metal at this stage has a mushy consistency due in part to the dispersion of the small dendrites 14 therein.
- the solidified product includes an inner portion 18 containing the small dendrites 14 at least partially surrounded by an outer portion.
- the thickness of the inner portion may be about 20 to about 30 percent of the thickness of the product.
- the small dendrites may be about 20 to about 50 microns in size and are substantially unworked by the casting apparatus and thus have a generally globular shape.
- molten metal in the inner layer 12 is squeezed in a direction opposite to its flow through a casting apparatus (as described in reference to casting between rolls) and/or may be forced into the outer layers 6 and 8 and reach the exterior surfaces of the outer layers 6 and 8.
- This feature of squeezing and/or forcing the molten metal in the inner layer occurs in any of the casting apparatuses described herein.
- Breakage of the dendrites in the inner layer in step 104 is achieved when casting between rolls by the shear forces resulting from speed differences between the inner layer of molten metal and the outer layer.
- Roll casters operated at conventional speeds of less than 3.3 m/min (10 feet per minute) do n ot generate the s hear forces required t o break any such dendrites.
- high speed (at least 8.2 m/min (25 feet per minute)) operation of a conventional roll caster with control of solidification a s described above allows for casting in the regime of the present invention, other conventional casting apparatuses may also be adapted for operating in a manner which results in the process of the invention.
- An important aspect of the present invention is breakage of dendrites in the inner layer.
- Breakage of the dendrites minimizes or avoids centerline segregation and results in improved formability and elongation properties in the finished product by virtue of the reduction or absence of coarse constituents as would be present in conventional roll cast or belt cast product exhibiting centerline segregation.
- Other suitable mechanisms for breaking dendrites in the inner layer include application to the liquid of mechanical stirring (e.g., propeller), electromagnetic stirring including rotational stator stirring and linear stator stirring, and high frequency ultrasonic vibration.
- the casting surfaces serve as heat sinks for the heat of the molten metal.
- heat is transferred from the molten metal to the cooled casting surface in a uniform manner to ensure uniformity in the surface of the cast product
- the cooled casting surfaces may be made from steel or copper and may be textured and include surface irregularities which contact the molten metal.
- the surface irregularities may serve to increase the heat transfer from the surfaces of the cooled casting surfaces. Imposition of a controlled degree of non-uniformity in the surfaces of the cooled casting surfaces can result in uniform heat transfer across the surfaces thereof.
- the surface irregularities may be in the form of grooves, dimples, knurls or other structures and may be spaced apart in a regular pattern of about 8 to 47 surface irregularities per cm (about 20 to about 120 surface irregularities per inch) or about 24 irregularities per cm (60 irregularities per inch).
- the surface irregularities may have a height of about 5 to about 50 microns or about 30 microns.
- the cooled casting surfaces may be coated with a material such as chromium or nickel to enhance separation of the cast product therefrom.
- the casting surfaces generally heat up during casting and are prone to oxidation at elevated temperatures.
- Non-uniform oxidation of the casting surfaces during casting can change the heat transfer properties thereof.
- the casting surfaces may be oxidized prior to use to minimize changes thereof during casting.
- Brushing the casting surfaces from time to time or continuously is beneficial in removing debris which builds up during casting of non-ferrous alloys. Small pieces of the cast product may break free from the product and adhere to the casting surfaces. These small pieces of non-ferrous alloy product are prone to oxidation, which result in non-uniformity in the heat transfer properties of the casting surfaces. Brushing of the casting surfaces avoids the non-uniformity problems from debris which may collect on the casting surfaces.
- the control, maintenance and selection of the appropriate speed of the rolls R 1 and R 2 may impact the operability of the present invention.
- the roll speed determines the speed that the molten metal M advances towards the nip N. If the speed is too slow, the large dendrites 10 will not experience sufficient forces to become entrained in the central portion 12 and break into the small dendrites 14. Accordingly, the present invention is suited for operation at high speeds such as about 7.62 to about 122 m/min (25 to about 400 feet per minute) or about 30.5 to 122 m/min (100 to about 400 feet per minute) or about 46 to about 91 m/min (150 to about 300 feet per minute).
- the linear rate per unit area that molten aluminum is delivered to the rolls R 1 and R 2 may be less than the speed of the rolls R 1 and R 2 or about one quarter of the roll speed.
- High-speed continuous casting according to the present invention may be achievable in part because the textured surfaces D 1 and D 2 ensure uniform heat transfer from the molten metal M.
- the roll separating force m ay b e an important parameter in practising the present invention.
- a significant benefit of the present invention is that solid strip is not produced until the metal reaches the nip N.
- the thickness is determined by the dimension of the nip N between the rolls R 1 and R 2 .
- the roll separating force may be sufficiently great to squeeze molten metal upstream and away from the nip N. Excessive molten metal passing through the nip N may cause the layers of the upper and lower shells 6 and 8 and the solid central portion 18 to fall away from each other and become misaligned. Insufficient molten metal reaching the nip N causes the strip to form prematurely as occurs in conventional roll casting processes.
- a prematurely formed strip 20 may be deformed by the rolls R 1 and R 2 and experience centerline segregation.
- Suitable roll separating forces are about 44 to about 525 N/cm (about 25 to about 300 pounds per inch) of width cast or about 175 N per cm (100 pounds per inch) of width cast.
- slower casting speeds may be needed when casting thicker gauge non-ferrous alloy in order to remove the heat from the thick alloy. Unlike conventional roil casting, such slower casting speeds do not result in excessive roll separating forces in the present invention because fully solid non-ferrous strip is not produced upstream of the nip.
- Non-ferrous alloy strip may be produced at thicknesses of about 0.25 cm (0.1 inch) or less (e.g., 0.152 cm (0.06 inch)) at casting speeds of about 7.62 to about 1.22 m/min) about 25 to about 400 feet per minute).
- Thicker gauge non-ferrous alloy strip may also be produced using the method of the present invention, for example at a thickness of about 0.63 cm (0.25 inch). Casting at linear rates contemplated by the present invention (i.e., about 25 to about 400 feet per minute) solidifies the non-ferrous alloy product about 1000 times faster than non-ferrous alloy cast as an ingot and improves the properties of the product over non-ferrous alloys cast as an ingot.
- the non-ferrous alloy product produced by method of the invention includes an inner portion substantially surrounded by an outer portion.
- the concentration of alloying elements may differ between the inner portion and the outer portion.
- the molten alloy may have an initial concentration of alloying elements including peritectic forming alloying elements and eutectic forming alloying elements.
- the concentration of alloying elements may differ between the outer portion and the inner portion.
- the inner portion of the product may be depleted in certain elements (such as eutectic formers) and enriched in other elements (such as peritectic formers) in comparison to the concentration of the eutectic formers and the peritectic formers in each of the metal and the outer portion.
- the grains in the non-ferrous alloy product of the present invention are substantially undeformed, i.e., have an equiaxial structure, such as globular. In the absence of hard particles in the inner portion of the product, centerline segregation and cracking typical in many cast non-ferrous alloys is minimized or avoided.
- One support mechanism shown in Fig. 5 includes a continuous conveyor belt B positioned beneath a strip S exiting rolls R 1 and R 2 , The belt B travels around pulleys P and supports the strip S for a distance that may be about 3.05 m (10 feet). The length of the belt B between the pulleys P may be determined by the casting process, the exit temperature of the strip S and the alloy of the strip S. Suitable materials for the belt B include fiberglass and metal (e.g., steel) in solid form or as a mesh. Alternatively, as shown in Fig.
- the support mechanism may include a stationary support surface J such as a metal shoe over which the strip S travels while it cools.
- the shoe J may be made of a material to which the hot strip S does not readily adhere.
- the strip S may be cooled at locations E with a fluid such as air or water.
- the strip S exits the rolls R 1 and R 2 at about 593°C (1100° F), and it may be desirable to lower the aluminum alloy strip temperature to about 538°C (1000° F) within about 20.3 to 25.4 cm (8 to 10 inches) of nip N.
- a fluid such as air or water.
- the strip S exits the rolls R 1 and R 2 at about 593°C (1100° F), and it may be desirable to lower the aluminum alloy strip temperature to about 538°C (1000° F) within about 20.3 to 25.4 cm (8 to 10 inches) of nip N.
- One suitable mechanism for cooling the strip at locations E to achieve that amount of colling is described in U.S. Patent No. 4,823,86
- Example 1 shows properties obtained in the as-rolled condition after coil cooling. The combination of high strength and good formability (elongation) is notable. The combination of high yield strength and elongation achieved in Examples 1 and 2 has heretofore not been achieved in 5xxx series aluminum-magnesium alloys. Bay way of comparison, aluminum alloy 5182, at best, has a yield strength of 372 MPa (54 ksi) and elongation of 7%.
- non-ferrous cast alloy products may be produced with improved yield strength and elongation compared to conventional cast products. Such improved properties allow for production of thinner product that is desirable in the market.
- the product exiting the casting apparatus may be shaped, such as by subsequent rolling, into another form or otherwise treated to manufacture can sheet, tab stock, automotive sheet and other end products including lithographic sheet and bright sheet.
- Subsequent processing of the product exiting the casting apparatus may be done by in-line rolling to benefit from the heat in the as-cast sheet (per the following U.S. Patent Nos.5,772,799 ; 5,772,802 ; 5,356,495 ; 5,496,423 ; 5,514,228 ; 5;470;405 ; 6,344,096 and 6,280,543 ).
- the as-cast sheet may be cooled and rolled subsequently off-line.
- Other processing of the sheet may be performed according to one or more of the aforesaid patents.
- the product may be in the form of sheet, plate, slab, foil, wire, rod, bar or extrusion.
Description
- The present invention relates to casting of non-ferrous metal alloys, more particularly, to casting non-ferrous metal alloys to create a rapidly solidified shell or shells and a segregation-free center zone containing broken dendrites.
- Continuous casting of metals such as aluminum alloys is conventionally performed in twin roll casters, block casters and belt casters. Twin roll casting of aluminum alloys has enjoyed good success and commercial application despite the relatively low production rates achievable to date. Twin roll casting traditionally is a combined solidification and deformation technique involving feeding molten metal into the bite between a pair of counter-rotating cooled rolls wherein solidification is initiated when the molten metal contacts the rolls. Solidified metal forms as a "freeze front" of the molten metal within the roll bite and solid metal' advances towards the nip, the point of minimum clearance between the rolls. The solid metal passes through the nip as a solid sheet. The solid sheet is deformed by the rolls (hot rolled) and exits the rolls.
- Aluminum alloys have successfully been roll cast into 0.63 cm (¼inch) thick sheet at at about 1-22 - 1.83 m/min (4-6 feet per minute) or about 0.89 - 1.25 kg per hour per cm of cas width (50-70 pounds per hour per inch of cast width (lbs/hr/in)). Attempts to increase the speed of roll casting typically fail due to centerline segregation. Although it is generally accepted that reduced gauge sheet (e.g., less than about 0.63 cm (¼ inch) thick) potentially could be produced more quickly than higher gauge sheet in a roll caster, the ability to roll cast aluminum at rates significantly above about 1.25 kg/hr/cm (70 lbs/hr/in) has been elusive.
- Typical operation of a twin roll caster at thin gauges is described in
U.S. Patent No. 5,518,064 and depicted inFigs. 1 and 2 . A molten metal holding chamber H is connected to a feed tip T which distributes molten metal M between water-cooled twin rolls R1 and R2 rotating in the direction of the arrows A1 and A2, respectively. The rolls R1 and R2 have respective smooth surfaces U1 and U2; any roughness thereon is an artifact of the roll grinding technique employed during their manufacture. The centerlines of the rolls R1 and R2 are in a vertical or generally vertical plane L (e.g., up to about 15° from vertical) such that the cast strip S forms in a generally horizontal path. Other versions of this method produce strip in a vertically upward direction. The width of the cast strip S is determined by the width of the tip T. The plane L passes through a region of minimum clearance between the rolls R1 and R2 referred to as the roll nip N. A solidification region exists between the solid cast strip S and the molten metal M and includes a mixed liquid-solid phase region X. A freeze front F is defined between the region X and the cast strip S as a line of complete solidification. - In conventional roll casting of aluminum alloys, the heat of the molten metal M is transferred to the rolls R1 and R2 such that the location of the freeze front F is maintained upstream of the nip N. In this manner, the molten metal M solidifies at a thickness greater than the dimension of the nip N. The solid cast strip S is deformed by the rolls R1 and R2 to achieve the final strip thickness. Hot rolling of the solidified strip between the rolls R1 and R2 according to conventional roll casting produces unique properties in the strip characteristic of roll cast aluminum alloy strip. In particular, a central zone through the thickness of the strip becomes enriched in eutectic forming elements (eutectic formers) in the alloy such as Fe, Si, Ni, Zn and the like and depleted in peritectic forming elements (Ti, Cr, V and Zr). This enrichment of eutectic formers (i.e., alloying elements other than Ti, Cr, V and Zr) in the central zone occurs because that portion of the strip S corresponds to a region of the freeze front F where solidification occurs last and is known as "centerline segregation". Extensive centerline segregation in the as-cast strip is a factor that restricts the speed of conventional roll casters. The as-cast strip also shows signs of working by the rolls. Grains which form during solidification of the metal upstream of the nip become flattened by the rolls. Therefore, roll cast aluminum includes grains elongated at an angle to the direction of rolling.
- The roll gap at the nip N may be reduced in order to produce thinner gauge strip S. However, as the roll gap is reduced, the roll separating force generated by the solid metal between the rolls R1 and R2 increases. The amount of roll separating force is affected by the location of the freeze front F in relation to the roll nip N. As the roll gap is reduced, the percentage reduction of the metal sheet is increased, and the roll separating force increases. At some point, the relative positions of the rolls R1 and R2 to achieve the desired roll gap cannot overcome the roll separating force, and the minimum gauge thickness has been reached for that position of the freeze front F.
- The roll separating force may be reduced by increasing the speed of the rolls in order to move the freeze front F downstream towards the nip N. When the freeze front is moved downstream (toward the nip N), the roll gap may be reduced. This movement of the freeze front F decreases the ratio between the thickness of the strip at the initial point of solidification and the roll gap at the nip N, thus decreasing the roll separating force as proportionally less solidified metal is being compressed and hot rolled. In this manner, as the position of the freeze front F moves toward the nip N, a proportionally greater amount of metal is solidified and then hot rolled at thinner gauges. According to conventional practice, roll casting of thin gauge strip is accomplished by first roll casting a relatively high gauge strip, decreasing the gauge until a maximum roll separating force is reached, advancing the freeze front to lower the roll separating force (by increasing the roll speed) and further decreasing the gauge until the maximum roll separating force is again reached, and repeating the process of advancing the freeze front and decreasing the gauge in an iterative manner until the desired thin gauge is achieved. For example, a 10 millimeter strip S may be rolled and the thickness may be reduced until the roll separating force becomes excessive (e.g., at 6 millimeters), necessitating a roll speed increase.
- This process of increasing the roll speed can only be practiced until the freeze front F reaches a predetermined downstream position. Conventional practice dictates that the freeze front F not progress forward into the roll nip N to ensure that solid strip is rolled at the nip N. It has been generally accepted that rolling of a solid strip at the nip N is needed to prevent failure of the cast metal strip S being hot rolled and to provide sufficient tensile strength in the exiting strip S to withstand the pulling force of a downstream winder, pinch rolls or the like. Consequently, the roll separating force of a conventionally operated twin roll caster in which a solid strip of aluminum alloy is hot rolled at the nip N is on the order of several tons per inch of width. Although some reduction in gauge is possible, operation at such high roll separating forces to ensure deformation of the strip at the nip N makes further reduction of the strip gauge very difficult. The speed of a roll caster is restricted by the need to maintain the freeze front F upstream of the nip N and prevent centerline segregation. Hence, the roll casting speed for aluminum alloys has been relatively low.
- Some reduction in roll separating force to obtain acceptable microstructure in aluminum alloys having high alloying element content is described in
U.S. Patent No. 6,193,818 . Alloys having 0.5 to 13 wt.% Si are roll cast into strip about 0.15 to 0.5 cm (0.05 to 0.2 inch) thick at roll separating forces of about 8757 to 70053 N/cm (5000 to 40,000 lbs/in) at speeds of about 1.7 m/cm to 3 m/min (5 to 9 feet per minute). While this represents an advance in roll separating force reduction, these forces still pose significant process challenges. Moreover, the productivity remains compromised and strip produced according to the 818 patent apparently exhibits some centerline segregation and grain elongation as shown inFig. 3 thereof. - A major impediment to high-speed roll casting is the difficulty in achieving uniform heat transfer from the molten metal to the smooth surfaces U1 and U2, i.e., cooling of the molten metal. In actuality, the surfaces U1 and U2 include various imperfections which alter the heat transfer properties of the rolls. At high rolling speeds, such non-uniformity in heat transfer becomes problematic. For example, areas of the surfaces U1 and U2 with proper heat transfer will cool the molten metal M at the desired location upstream of the nip N whereas areas with insufficient heat transfer properties will allow a portion of the molten metal to advance beyond the desired location and create non-uniformity in the cast strip.
- Thin gauge steel strip has been successfully roll cast in vertical casters at high speeds (up to about 122 m/min (400 feet per minute)) and low roll separating forces. The rolls of a vertical roll caster are positioned side by side so that the strip forms in a downward direction. In this vertical orientation, molten steel is delivered to the bite between the rolls to form a pool of molten steel. The upper surface of the pool of molten steel is often protected from the atmosphere by means of an inert gas.
- While vertical twin roll casting from a pool of molten metal is successful for steel, vertical casting of alloys sensitive to oxidation (e.g., aluminum) requires additional control. One suggestion for overcoming this problem of oxidized aluminum in vertical roll casting on a laboratory scale is described in Haga et al., "High Speed Roll C aster for Aluminum Alloy Strip", Proceedings of ICAA-6, Aluminum Alloys, Vol. 1, pp. 327-332 (1998). According to that method, a stream of molten aluminum alloy is ejected from a gas-pressurized nozzle directly onto one or both of the twin rolls in a vertical roll caster. Although high speed casting of aluminum alloy strip is reported, a m ajor drawback t o this technique i s that the delivery rate of the molten aluminum alloy must be carefully controlled to ensure uniformity in the cast strip. When a single stream is ejected onto a roll, that stream is solidified into the strip. If a stream is ejected onto each roll, each stream becomes one half of the thickness of the cast strip. In both cases, any variation in the gas pressure or delivery rate of the molten aluminum alloy results in non-uniformity in the cast strip. The control parameters for this type of aluminum alloy roll casting are not practical on a commercial scale.
- Continuous casting of aluminum alloys has been achieved on belt casters at rates of about 6.1 to 7.6 m/min (20-25 feet per minute) at about ¾ inch (19 mm) gauge reaching a productivity level of about 250 kg per hr. per cm of width (400 pounds per hour per inch of width). In conventional belt casting as described in
U.S. Patent No. 4,002,197 molten metal is fed into a casting region between opposed portions of a pair of revolving flexible metal belts. Each of the two flexible casting belts revolves in a path defined by upstream rollers located at one end of the casting region and downstream rollers located at the other end of the casting region. In this manner, the casting belts converge directly opposite each other around the upstream rollers to form an entrance to the casting region in the nip between the upstream rollers. The molten metal is fed directly into the nip. The molten metal is confined between the moving belts and is solidified as it is carried along. Heat liberated by the solidifying metal is withdrawn through the portions of the two belts which are adjacent to the metal being cast This heat is withdrawn by cooling the reverse surfaces of the belts by means of rapidly moving substantially continuous films of water flowing against and communicating with these reverse surfaces. - The operating parameters for belt casting are significantly different from those for roll casting. In particular, there is no intentional hot rolling of the strip. Solidification of the metal is completed in a distance of about 12-15 inches (30-38 mm) downstream of the nip for a thickness of 1.89 cm (¾ inch). The belts are exposed to high temperatures when contacted by molten metal on one surface and are cooled by water on the inner surface. This may lead to distortion of the belts. The tension in the belt must be adjusted to account for expansion or contraction of the belt due to temperature fluctuations in order to achieve consistent surface quality of the strip. Casting of aluminum alloys on a belt caster has been used to d ate mainly for products having minimal surface quality requirements or for products which are subsequently painted.
- The problem of thermal instability of the belts is avoided in block casters. Block casters include a plurality of chilling blocks mounted adjacent to each other on a pair of opposing tracks. Each set of chilling blocks rotates in the opposite direction to form a casting region therebetween into which molten metal is delivered. The chilling blocks act as heat sinks as the heat of the molten metal transfers thereto. Solidification of the metal is complete about 30 - 37.5 cm (12-15 inches) downstream of the entrance to the casting region at a thickness of 1.875 cm (¾ inch). The heat transferred to the chilling blocks is removed during the return loop. Unlike belts, the shilling blocks are not functionally distorted by the heat transfer. However, block casters require precise dimensional control to prevent gaps between the blocks which cause non-uniformity and defects in the cast strip.
- This concept of transferring the heat of the molten metal to a casting surface has been employed in certain modified belt casters as described in
U.S. Patent Nos. 5,515,908 and5,564,491 . In a heat sink belt caster, molten metal is delivered to the belts (the casting surface) upstream of the nip with solidification initiating prior to the nip and continued heat transfer from the metal to the belts downstream of the nip. In this system, molten metal is supplied to the belts along the curve of the upstream rollers so that the metal is substantially solidified by the time it reaches the nip between the upstream rollers. The heat of the molten metal and the cast strip is transferred to the belts within the casting region (including downstream of the nip). The heat is then removed from the belts while the belts are out of contact with either of the molten metal or the cast strip. In this manner, the portions of the belts within the casting region (in contact with the molten metal and cast strip) are not subjected to large variations in temperature as occurs in conventional belt casters. The thickness of the strip can be limited by the heat capacity of the belts between which casting takes place. Production rates of 429 kg/hr/cm (2400 lbs/hr/in) for 0.08-0.1 inch (2-2.5 mm) strip have been achieved. - However, problems associated with the belts used in conventional belt casting remain. In particular, uniformity of the cast strip depends on the stability of (i.e., tension in) the belts. For any belt caster, conventional or heat sink type, contact of hot molten metal with the belts and the heat transfer from the solidifying metal to the belts creates instability in the belts. Further, belts need to be changed at regular intervals which disrupts production.
- Strip material of non-ferrous alloys are desirable for use as sheet product in the automotive and aerospace industries and in the production of can bodies and can end and tab stock. Conventional manufacturing of can body stock employs batch processes which include an extensive sequence of separate steps. When an ingot i s needed for further processing, it is first scalped, heat treated to homogenize the alloy, cooled and rolled while still hot in a number of passes, hot finish rolled, and finally coiled, air cooled and stored. The coil may be annealed in a batch step. The coiled sheet stock is then further reduced to final gauge by cold rolling using unwinders, rewinders and single and/or tandem rolling mills. These batch processes typically used in the aluminum industry require many different material handling operations to move ingots and coils between what are typically separate processing steps.
- Efforts to streamline production of can body stock are described in
U.S. Patent Nos. 4,260,419 via direct chill casting and4,282,044 via minimill continuous strip casting. Both processes require many material handling operations to move ingots and coils. Such operations are labor intensive, consume energy and frequently result in product damage. -
U. S. Patent Nos. 5,772 ,802 and5,772 ,799 disclose belt casting methods in which can or lid stock and a method for its manufacture in which a low alloy content aluminum alloy is strip cast to form a hot strip cast feedstock, the hot feedstock is rapidly quenched to prevent substantial precipitation, annealed and quenched rapidly to prevent substantial precipitation of alloying elements and then cold rolled. This process has been successful despite the relatively low production rates achievable to date. -
US-2,693,012 discloses a process for fabricating sheet stock from molten metal. Molten metal is fed continuously to the bight of a pair of cooled rolls driven at high rotation speed to produce a sheet with thickness 1.65 mm. As the metal is cooled on the surface of the roll a retaining skin of metal adjacent to the roll is formed and a plastic condition in the central portion of the remaining metal is created. The plastic metal is mechanically worked and finally frozen completely immediately before the instant the sheet metal passes through the bight of the rolls. - In addition, alloys other than aluminum such as magnesium alloys have not been continuously cast on a commercial scale. Magnesium metal has a hexagonal crystal structure that severely restricts the amount of deformation that can be applied, particularly at low temperatures. Production of wrought magnesium alloy products is therefore normally carried out by hot working in the range of 300 -500 C. Even under those conditions, a multitude of rolling passes and intermediate anneals are needed. In the conventional ingot method, a total of up to 25 rolling passes with intermediate anneals are used to make a finished product of 0.5 mm gauge. As a result, magnesium wrought products tend to be expensive.
- Accordingly, a need remains for a cost-effective method of casting of non-ferrous alloys that achieves uniformity in the cast surface.
- According to the present invention, there is provided a method of continuously casting molten metal into a metal product comprising the steps of:
- providing non-ferrous molten metal to a pair of spaced apart advancing casting surfaces;
- solidifying the molten metal on the casting surfaces while advancing the metal between the casting surfaces to produce solid metal outer layers adjacent the casting surfaces and a semi-solid inner layer containing globular dendrites of the metal between the solid metal outer layers;
- solidifying the semi-solid inner layer to produce a solid metal product comprised of the inner layer and the outer layers; and
- withdrawing the solid metal product from between the casting surfaces, the casting surfaces being surfaces of rotating rolls with a nip defined therebetween or
- the casting surfaces being surfaces of belts travelling over rotating rolls, the rolls defining a nip therebetween, characterised in that the metal is an alloy of magnesium, titanium, copper, nickel, zinc or tin and in that product is made to exit the nip at a rate of 25 to 400 feet per minute (7.6 to 122 metres per minute); the force applied by the rolls to the metal advancing therebetween is no greater than 300 lbs per inch of width of the product, (525 N per cm. of width of the product), and the product comprises a metal strip having a thickness of 0.06 to 0.25 inches (0.15 to 0.64 cm.), the method being conducted such that completion of said solidifying step occurs at the nip, and in which method the dendrites are broken in the semi-solid inner layer prior to completion of said solidifying step and wherein said dendrites are unworked.
- Preferably, the metal is an alloy of magnesium or titanium.
- Advantageously, the product exits the nip at least 30.5 metres per minute (100 feet per minute).
- Conveniently, the thickness of the solidified inner layer comprises 20% to 30% of thickness of the product.
- Preferably, the casting surfaces are textured to provide surface irregularities which contact the molten metal.
- Advantageously, said surface irregularities are in the form of grooves, dimples or knurls.
- Conveniently, said surface irregularities are spaced apart in a regular pattern of 20 to 120 irregularities per inch (8 to 48 irregularities per cm.)
- Preferably, said surface irregularities are spaced apart in a regular pattern of 60 irregularities per inch (24 irregularities per cm.)
- Conveniently, said surface irregularities have a height of 5 to 50 micrometres.
- Advantageously, said surface irregularities have a height of 30 micrometres.
- Preferably, the casting surfaces are continuously brushed in regions remote from the product to remove debris which might build up.
- A complete understanding of the invention will be obtained from the following description when taken in connection with the accompanying drawing figures wherein like reference characters identify like parts throughout.
-
Fig. 1 is a schematic of a portion of a caster with a molten metal delivery tip and a pair of rolls; -
Fig. 2 is an enlarged cross-sectioned schematic of the molten metal delivery tip and rolls shown inFig. 1 operated according to the prior art; -
Fig. 3 is flow chart of steps of the casting method of the present invention; -
Fig.4 is a schematic of molten metal casting operated according to the present invention -
Fig. 5 is a schematic of a caster made in accordance with the present invention with a strip support mechanism and optional cooling means; and -
Fig. 6 is a schematic of a caster made in accordance with the present invention with another strip support mechanism and optional cooling means. - For purposes of the description hereinafter, it is to be understood that the invention may assume various alternative variations and step sequences, except where expressly specified to the contrary. It is also to he understood that the specific devices and processes illustrated in the attached drawings, and described in the following specifications are simply exemplary embodiments of the invention. Hence, specific dimensions and other physical characteristics related to the embodiments disclosed herein are not to be considered as limiting. When referring to any numerical range of values, such ranges are understood to include each and every number and/or fraction between the stated range minimum and maximum.
- The present invention includes a method of casting non-ferrous alloy which includes delivering molten non-ferrous alloy to a casting apparatus. By non-ferrous alloy it is meant an alloy of an element such as magnesium, titanium, copper, nickel, zinc or tin. Particularly suitable non-ferrous alloys for use in the present invention are magnesium alloys and titanium alloys.
- The phrases "magnesium alloys" and "titanium alloys" are intended to mean alloys containing at least 50 wt% of the stated element and at least one modifier element. Magnesium, and titanium alloys are considered attractive candidates for structural use in aerospace and automotive industries because of their light weight, high strength to weight ratio, and high specific stiffness at both room and elevated temperatures. Examples of systems of magnesium based alloys are Mg-Al system; Mg-Al-Zn system; Mg-Al-Si system; Mg-Al-Rare Earth (RE) system; Mg-Th-Zr system; Mg-Th-Zn-Zr system; Mg-Zn-Zr system; and Mg-Zn-Zr-RE system.
- The invention in its most basic form is depicted schematically in the flow chart of
Fig. 3 . Instep 100, molten non-ferrous metal is delivered to a casting apparatus. The casting apparatus includes a pair of spaced apart advancing casting surfaces such as described in detail below. Instep 102, the casting apparatus rapidly cools at least a portion of the non-ferrous alloy to solidify an outer layer of the non-ferrous alloy while maintaining a semi-solid inner layer. The inner layer includes a molten metal component and a solid component of dendrites of the metal. The solidified outer layer increases in thickness as the alloy is cast. The dendrites of the inner layer are altered instep 104, such as by breaking the dendrites into smaller structures. Instep 106, the inner layer is solidified. The product exiting the casting apparatus includes the solid inner layer formed instep 106 containing the broken dendrites sandwiched, within the outer solid layer of alloy. The product may bein various forms such as but not limited to sheet, plate, slab, and foil. For extrusion type casting, the product may be in the form of a wire, rod, bar or other extrusion. In either case, the product may be further processed and/or treated instep 108. The order of steps 100-108 are not fixed in the method of the present invention and may occur sequentially or some of the steps may occur simultaneously. - The present invention balances the rate of solidification of the molten metal, the formation of dendrites in the solidifying metal and alteration of the dendrites to obtain desired properties in the final product. The cooling rate is selected. to achieve rapid solidification of the outer layers of the metal. For non-ferrous alloys, cooling of the outer layers of metal may occur at a rate of at least about 100° C per minute. Suitable casting apparatuses include cooled casting surfaces such as in a twin roll caster, a belt caster, a slab caster, or a block caster. Vertical roll casters may also be used in the present invention. In a continuous caster, the casting surfaces generally are spaced apart and have a region at which the distance therebetween is at a minimum. In a roll caster, the region of minimum distance between casting surfaces is the nip. In a belt caster, the region of minimum distance between casting surfaces of the belts may be the nip between the entrance pulleys of the caster. As is described in more detail below, operation of a casting apparatus in the regime of the present invention involves solidification of the metal at the location of a minimum distance between the casting surfaces. While the method of present invention is described below as performed using a twin roll caster, this is not meant to be limiting. Other continuous casting surfaces may be used to practice the invention.
- By way of example, a roll caster (
Fig. 1 ) may be operated to practice the present invention as shown in detail inFig. 4 . Referring toFig. 1 (which generically depicts horizontal continuous casting according to the prior art and according to the present invention), the present invention is practiced using a pair of counter-rotating cooled rolls R1 and R2 rotating in the directions of the arrows A1 and A2, respectively. By the term horizontal, it is meant that the cast strip is produced in a horizontal orientation or at an angle of plus or minus about 30° from horizontal. As shown in more detail inFig. 3 , a feed tip T, which may be made from a refractory or other ceramic material, distributes molten metal M in the direction of arrow B directly onto the rolls R1 and R2 rotating in the direction of the arrows A1 and A2, respectively. Gaps G1 and G2 between the feed tip T and the respective rolls R1 and R2 are maintained as small as possible to prevent molten metal from leaking out and to minimize the exposure of the molten metal to the atmosphere along the rolls R1 and R2 yet avoid contact between the tip T and the rolls R1 and R2. A suitable dimension of the gaps G1 and G2 is about 0.01 inch (0.25 mm). A plane L through the centerline of the rolls R1 and R2 passes through a region of minimum clearance between the rolls R1 and R2 referred to as the roll nip N. - Molten metal M is provided to the casting surfaces of the roll caster, the cooled rolls R1 and R2. The molten metal M directly contacts the rolls R1 and R2 at regions 2 and 4, respectively. Upon contact with the rolls R1 and R2, the metal M begins to cool and solidify. The cooling metal solidifies as an upper shell 6 of solidified metal adjacent the roll R1 and a
lower shell 8 of solidified metal adjacent to the roll R2. The thickness of theshells 6 and 8 increases as the metal M advances towards the nip N.Large dendrites 10 of solidified metal (not shown to scale) are produced at the interfaces between each of the upper andlower shells 6 and 8 and the molten metal M. Thelarge dendrites 10 are broken and dragged into acenter portion 12 of the slower moving flow of the molten metal M and are carried in the direction of arrows C1 and C2. The dragging action of the flow can cause thelarge dendrites 10 to be broken further into smaller dendrites 14 (not shown to scale). In thecentral portion 12 upstream of the nip N referred to asregion 16, the metal M is semi-solid and includes a solid component (the solidified small dendrites 14) and a molten metal component. The metal M in theregion 16 has a mushy consistency due in part to the dispersion of the small dendrites 14 therein. At the location of the nip N, some of the molten metal is squeezed backwards in a direction opposite to the arrows C1 and C2. The forward rotation of the rolls R1 and R2 at the nip N advances substantially only the solid portion of the metal (the upper andlower shells 6 and 8 and the small dendrites 14 in the central portion 12) while forcing molten metal in thecentral portion 12 upstream from the nip N such that the metal is completely solid as it leaves the point of the nip N. Downstream of the nip N, thecentral portion 12 is a solidcentral layer 18 containing the small dendrites 14 sandwiched between the upper shell 6 and thelower shell 8. In thecentral layer 18, the small dendrites 14 may be about 20 to about 50 microns in size and have a generally globular shape. In a strip product, the solid inner portion may constitute about 20 to about 30 percent of the total thickness of the strip. While the caster ofFig. 4 is shown as producing strip S in a generally horizontal orientation, this is not meant to be limiting as the strip S may exit the caster at an angle or vertically. - The casting process described in relation to
Fig. 4 follows the method steps outlined above. Molten metal delivered instep 100 to the roll caster begins to cool and solidify instep 102. The cooling metal develops outer layers of solidifiedmetal 6 and 8 near or adjacent the cooled casting surfaces (R1 and R2). The thickness of the solidifiedlayers 6 and 8 increases as the metal advances through the casting apparatus. Perstep 102,dendrites 10 form in the metal in aninner layer 12 that is at least partially surrounded by the solidifiedouter layers 6 and 8. InFig. 4 , theouter layers 6 and 8 substantially surround theinner layer 12 as a sandwich of theinner layer 12 between the twoouter layers 6 and 8. In other casting apparatuses the outer layer may completely surround the inner layer. Instep 104, thedendrites 10 are altered, e.g., broken into smaller structures 14. In theinner layer 12 prior to complete solidification of the metal, the metal is semi-solid and includes a solid component (the solidified small dendrites 14) and a molten metal component. The metal at this stage has a mushy consistency due in part to the dispersion of the small dendrites 14 therein. Instep 106 at the location of complete solidification of the metal in the casting apparatus, the solidified product includes aninner portion 18 containing the small dendrites 14 at least partially surrounded by an outer portion. The thickness of the inner portion may be about 20 to about 30 percent of the thickness of the product. In the inner portion, the small dendrites may be about 20 to about 50 microns in size and are substantially unworked by the casting apparatus and thus have a generally globular shape. - According to the present invention, molten metal in the
inner layer 12 is squeezed in a direction opposite to its flow through a casting apparatus (as described in reference to casting between rolls) and/or may be forced into theouter layers 6 and 8 and reach the exterior surfaces of theouter layers 6 and 8. This feature of squeezing and/or forcing the molten metal in the inner layer occurs in any of the casting apparatuses described herein. - Breakage of the dendrites in the inner layer in
step 104 is achieved when casting between rolls by the shear forces resulting from speed differences between the inner layer of molten metal and the outer layer. Roll casters operated at conventional speeds of less than 3.3 m/min (10 feet per minute) do n ot generate the s hear forces required t o break any such dendrites. While high speed (at least 8.2 m/min (25 feet per minute)) operation of a conventional roll caster with control of solidification a s described above allows for casting in the regime of the present invention, other conventional casting apparatuses may also be adapted for operating in a manner which results in the process of the invention. An important aspect of the present invention is breakage of dendrites in the inner layer. Breakage of the dendrites minimizes or avoids centerline segregation and results in improved formability and elongation properties in the finished product by virtue of the reduction or absence of coarse constituents as would be present in conventional roll cast or belt cast product exhibiting centerline segregation. Other suitable mechanisms for breaking dendrites in the inner layer include application to the liquid of mechanical stirring (e.g., propeller), electromagnetic stirring including rotational stator stirring and linear stator stirring, and high frequency ultrasonic vibration. - The casting surfaces serve as heat sinks for the heat of the molten metal. In the present invention, heat is transferred from the molten metal to the cooled casting surface in a uniform manner to ensure uniformity in the surface of the cast product The cooled casting surfaces may be made from steel or copper and may be textured and include surface irregularities which contact the molten metal. The surface irregularities may serve to increase the heat transfer from the surfaces of the cooled casting surfaces. Imposition of a controlled degree of non-uniformity in the surfaces of the cooled casting surfaces can result in uniform heat transfer across the surfaces thereof. The surface irregularities may be in the form of grooves, dimples, knurls or other structures and may be spaced apart in a regular pattern of about 8 to 47 surface irregularities per cm (about 20 to about 120 surface irregularities per inch) or about 24 irregularities per cm (60 irregularities per inch). The surface irregularities may have a height of about 5 to about 50 microns or about 30 microns. The cooled casting surfaces may be coated with a material such as chromium or nickel to enhance separation of the cast product therefrom.
- The casting surfaces generally heat up during casting and are prone to oxidation at elevated temperatures. Non-uniform oxidation of the casting surfaces during casting can change the heat transfer properties thereof. Hence, the casting surfaces may be oxidized prior to use to minimize changes thereof during casting. Brushing the casting surfaces from time to time or continuously is beneficial in removing debris which builds up during casting of non-ferrous alloys. Small pieces of the cast product may break free from the product and adhere to the casting surfaces. These small pieces of non-ferrous alloy product are prone to oxidation, which result in non-uniformity in the heat transfer properties of the casting surfaces. Brushing of the casting surfaces avoids the non-uniformity problems from debris which may collect on the casting surfaces.
- In a roll caster operated in the regime of the present invention, the control, maintenance and selection of the appropriate speed of the rolls R1 and R2 may impact the operability of the present invention. The roll speed determines the speed that the molten metal M advances towards the nip N. If the speed is too slow, the
large dendrites 10 will not experience sufficient forces to become entrained in thecentral portion 12 and break into the small dendrites 14. Accordingly, the present invention is suited for operation at high speeds such as about 7.62 to about 122 m/min (25 to about 400 feet per minute) or about 30.5 to 122 m/min (100 to about 400 feet per minute) or about 46 to about 91 m/min (150 to about 300 feet per minute). The linear rate per unit area that molten aluminum is delivered to the rolls R1 and R2 may be less than the speed of the rolls R1 and R2 or about one quarter of the roll speed. High-speed continuous casting according to the present invention may be achievable in part because the textured surfaces D1 and D2 ensure uniform heat transfer from the molten metal M. - The roll separating force m ay b e an important parameter in practising the present invention. A significant benefit of the present invention is that solid strip is not produced until the metal reaches the nip N. The thickness is determined by the dimension of the nip N between the rolls R1 and R2. The roll separating force may be sufficiently great to squeeze molten metal upstream and away from the nip N. Excessive molten metal passing through the nip N may cause the layers of the upper and
lower shells 6 and 8 and the solidcentral portion 18 to fall away from each other and become misaligned. Insufficient molten metal reaching the nip N causes the strip to form prematurely as occurs in conventional roll casting processes. A prematurely formedstrip 20 may be deformed by the rolls R1 and R2 and experience centerline segregation. Suitable roll separating forces are about 44 to about 525 N/cm (about 25 to about 300 pounds per inch) of width cast or about 175 N per cm (100 pounds per inch) of width cast. In general, slower casting speeds may be needed when casting thicker gauge non-ferrous alloy in order to remove the heat from the thick alloy. Unlike conventional roil casting, such slower casting speeds do not result in excessive roll separating forces in the present invention because fully solid non-ferrous strip is not produced upstream of the nip. - Non-ferrous alloy strip may be produced at thicknesses of about 0.25 cm (0.1 inch) or less (e.g., 0.152 cm (0.06 inch)) at casting speeds of about 7.62 to about 1.22 m/min) about 25 to about 400 feet per minute). Thicker gauge non-ferrous alloy strip may also be produced using the method of the present invention, for example at a thickness of about 0.63 cm (0.25 inch). Casting at linear rates contemplated by the present invention (i.e., about 25 to about 400 feet per minute) solidifies the non-ferrous alloy product about 1000 times faster than non-ferrous alloy cast as an ingot and improves the properties of the product over non-ferrous alloys cast as an ingot.
- The non-ferrous alloy product produced by method of the invention includes an inner portion substantially surrounded by an outer portion. The concentration of alloying elements may differ between the inner portion and the outer portion. The molten alloy may have an initial concentration of alloying elements including peritectic forming alloying elements and eutectic forming alloying elements. The concentration of alloying elements may differ between the outer portion and the inner portion. The inner portion of the product may be depleted in certain elements (such as eutectic formers) and enriched in other elements (such as peritectic formers) in comparison to the concentration of the eutectic formers and the peritectic formers in each of the metal and the outer portion. The grains in the non-ferrous alloy product of the present invention are substantially undeformed, i.e., have an equiaxial structure, such as globular. In the absence of hard particles in the inner portion of the product, centerline segregation and cracking typical in many cast non-ferrous alloys is minimized or avoided.
- In practicing the present invention, it may be beneficial to support the product exiting the casting apparatus until the product cools sufficiently to be self. supporting. One support mechanism shown in
Fig. 5 includes a continuous conveyor belt B positioned beneath a strip S exiting rolls R1 and R2, The belt B travels around pulleys P and supports the strip S for a distance that may be about 3.05 m (10 feet). The length of the belt B between the pulleys P may be determined by the casting process, the exit temperature of the strip S and the alloy of the strip S. Suitable materials for the belt B include fiberglass and metal (e.g., steel) in solid form or as a mesh. Alternatively, as shown inFig. 6 , the support mechanism may include a stationary support surface J such as a metal shoe over which the strip S travels while it cools. The shoe J may be made of a material to which the hot strip S does not readily adhere. In certain instances where the strip S is subject to breakage upon exiting the rolls R1 and R2, the strip S may be cooled at locations E with a fluid such as air or water. Typically for aluminum alloys, the strip S exits the rolls R1 and R2 at about 593°C (1100° F), and it may be desirable to lower the aluminum alloy strip temperature to about 538°C (1000° F) within about 20.3 to 25.4 cm (8 to 10 inches) of nip N. One suitable mechanism for cooling the strip at locations E to achieve that amount of colling is described inU.S. Patent No. 4,823,860 - An aluminum alloy containing by wt% 0.75 Si, 0.20 Fe, 0.80 Cu, 0.25 Mn and 2.0 Mg was cast according to the present invention and then hot and cold rolled in-line to 0.038 cm (0.015 inch) gauge. The resultant properties for two products are listed in Table 1. Example 1 shows properties obtained in the as-rolled condition after coil cooling. The combination of high strength and good formability (elongation) is notable. The combination of high yield strength and elongation achieved in Examples 1 and 2 has heretofore not been achieved in 5xxx series aluminum-magnesium alloys. Bay way of comparison, aluminum alloy 5182, at best, has a yield strength of 372 MPa (54 ksi) and elongation of 7%. Example 2 shows properties obtained after the sheet was solution heat treated and aged at 135°C (275° F) in the laboratory. Good yield strength and superior bending properties were achieved.
Table 1 Property Example 1 Example 2 + Yield strength (ksi) 60 43 + UTS (ksi) 65 55 Elongation (%) 10 16 Bend radius (r/t) 1.7 0.3* Ludering lines none none Olsen height (in) - lubricated 0.195 - Corrosion - - Orange peel none none Finish semi-bright mill O-temper yes yes *Flat hem
+ 1 ksi = 6 · 9 MPa - By practicing the method of the present invention, non-ferrous cast alloy products may be produced with improved yield strength and elongation compared to conventional cast products. Such improved properties allow for production of thinner product that is desirable in the market.
- The product exiting the casting apparatus may be shaped, such as by subsequent rolling, into another form or otherwise treated to manufacture can sheet, tab stock, automotive sheet and other end products including lithographic sheet and bright sheet. Subsequent processing of the product exiting the casting apparatus may be done by in-line rolling to benefit from the heat in the as-cast sheet (per the following
U.S. Patent Nos.5,772,799 ;5,772,802 ;5,356,495 ;5,496,423 ;5,514,228 ;5;470;405 ;6,344,096 and6,280,543 ). Alternatively, the as-cast sheet may be cooled and rolled subsequently off-line. Other processing of the sheet may be performed according to one or more of the aforesaid patents. - Whereas the preferred embodiments of the present invention have been described above in terms of being especially valuable in producing non-ferrous alloy parts for the automotive and aerospace industries and the beverage can industries, it will be apparent to those skilled in the art that the present invention will also be valuable for producing parts such as boats, canoes, skis, pianos, harps, delivery truck bodies, truck cabs, buses, trash collectors bins, racing boat hulls, private aircraft parts, fire truck hose containers, material handling equipment, dock boards, portable ramps, aerospace equipment parts, including rockets and satellites, radar tracking systems, electronic equipment cabinets, vibratory screens, tote bins, luggage frames and sides, ladders, water h eater a nodes, typewriters, rocket launchers and mortar bases, textile machinery parts, concrete buckets and hand finishing tools, jigs and fixtures and vibration testing machines.
- Whereas the preferred embodiments of the present invention have been described above in terms of being especially valuable in horizontal casting of non-ferrous base alloys, it will be apparent to those skilled in the art that the present invention will also be valuable in vertical casting as well as any angle between vertical and horizontal casting.
- Whereas the preferred embodiments of the present invention have been described above in terms of aluminum metal strip product exiting the casting apparatus that includes a solid inner layer containing altered dendritic structures substantially surrounded by the outer solid layer of alloy, the product may be in the form of sheet, plate, slab, foil, wire, rod, bar or extrusion.
- Whereas the preferred embodiments of the present invention have been described above in terms of using the nip of twin rolls to break dendrites that form as the metal solidifies, that is aluminum metal, it will be apparent to those skilled in the art that the present invention will also be valuable with other non-ferrous metals including, titanium, magnesium, nickel, zinc, tin and copper.
Claims (11)
- A method of continuously casting molten metal into a metal product comprising the steps of:providing non-ferrous molten metal to a pair of spaced apart advancing casting surfaces;solidifying the molten metal on the casting surfaces while advancing the metal between the casting surfaces to produce solid metal outer layers adjacent the casting surfaces and a semi-solid inner layer containing globular dendrites of the metal between the solid metal outer layers;solidifying the semi-solid inner layer to produce a solid metal product comprised of the inner layer and the outer layers; andwithdrawing the solid metal product from between the casting surfaces, the casting surfaces being surfaces of rotating rolls with a nip defined therebetween or the casting surfaces being surfaces of belts travelling over rotating rolls, the rolls defining a nip therebetween, characterised in that the metal is an alloy of magnesium, titanium, copper, nickel, zinc or tin and in that product is made to exit the nip at a rate of 25 to 400 feet per minute (7.6 to 122 metres per minute); the force applied by the rolls to the metal advancing therebetween is no greater than 300 Ibs per inch of width of the product, (525 N per cm. of width of the product), and the product comprises a metal strip having a thickness of 0.06 to 0.25 inches (0.15 to 0.64 cm.), the method being conducted such that completion of said solidifying step occurs at the nip, and in which method the dendrites are broken in the semi-solid inner layer prior to completion of said solidifying step and wherein said dendrites are unworked.
- The method of Claim 1 wherein the metal is an alloy of magnesium or titanium.
- A method according to Claim 1 wherein the product exits the nip at at least 30.5 metres per minute (100 feet per minute).
- A method according to any preceding claim wherein the thickness the solidified inner layer comprises 20% to 30% of thickness of the product.
- A method according to any preceding claim wherein the casting surfaces are textured to provide surface irregularities which contact the molten metal.
- A method according to Claim 5 wherein said surface irregularities are in the form of grooves, dimples or knurls.
- A method according to Claim 5 or Claim 6 wherein said surface irregularities are spaced apart in a regular pattern of 20 to 120 irregularities per inch (8 to 48 irregularities per cm.)
- A method according to Claim 5 or Claim 6 wherein said surface irregularities are spaced apart in a regular pattern of 60 irregularities per inch (24 irregularities per cm.)
- A method according to any of Claims 5 to 8 wherein said surface irregularities have a height of 5 to 50 micrometres.
- A method according to any of Claims 5 to 8 wherein said surface irregularities have a height of 30 micrometres.
- A method according to any preceding claim wherein the casting surfaces are continuously brushed in regions remote from the product to remove debris which might build up.
Applications Claiming Priority (15)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US40533302P | 2002-08-21 | 2002-08-21 | |
US40535902P | 2002-08-21 | 2002-08-21 | |
US405359P | 2002-08-21 | ||
US405333P | 2002-08-21 | ||
US40650602P | 2002-08-28 | 2002-08-28 | |
US40650702P | 2002-08-28 | 2002-08-28 | |
US40650402P | 2002-08-28 | 2002-08-28 | |
US40645302P | 2002-08-28 | 2002-08-28 | |
US40650502P | 2002-08-28 | 2002-08-28 | |
US406504P | 2002-08-28 | ||
US406506P | 2002-08-28 | ||
US406453P | 2002-08-28 | ||
US406507P | 2002-08-28 | ||
US406505P | 2002-08-28 | ||
PCT/US2003/018764 WO2004018124A1 (en) | 2002-08-21 | 2003-06-13 | Casting of non-ferrous metals |
Publications (3)
Publication Number | Publication Date |
---|---|
EP1545812A1 EP1545812A1 (en) | 2005-06-29 |
EP1545812A4 EP1545812A4 (en) | 2006-04-05 |
EP1545812B1 true EP1545812B1 (en) | 2013-05-01 |
Family
ID=31950967
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP03737080.6A Expired - Lifetime EP1545812B1 (en) | 2002-08-21 | 2003-06-13 | Casting of non-ferrous metals |
Country Status (6)
Country | Link |
---|---|
EP (1) | EP1545812B1 (en) |
JP (1) | JP2005536354A (en) |
KR (2) | KR101129489B1 (en) |
AU (1) | AU2003236522A1 (en) |
ES (1) | ES2423825T3 (en) |
WO (1) | WO2004018124A1 (en) |
Families Citing this family (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AU2002951075A0 (en) * | 2002-08-29 | 2002-09-12 | Commonwealth Scientific And Industrial Research Organisation | Twin roll casting of magnesium and magnesium alloys |
CN100366380C (en) * | 2005-07-20 | 2008-02-06 | 哈尔滨工业大学 | Method of comtinuously preparing alloy semi solid rod and its device |
US8403027B2 (en) * | 2007-04-11 | 2013-03-26 | Alcoa Inc. | Strip casting of immiscible metals |
US7846554B2 (en) * | 2007-04-11 | 2010-12-07 | Alcoa Inc. | Functionally graded metal matrix composite sheet |
KR20100038809A (en) * | 2008-10-06 | 2010-04-15 | 포항공과대학교 산학협력단 | Magnesium alloy panel having high formability and method of manufacturing the same |
US8956472B2 (en) | 2008-11-07 | 2015-02-17 | Alcoa Inc. | Corrosion resistant aluminum alloys having high amounts of magnesium and methods of making the same |
CN103119185B (en) | 2010-09-08 | 2015-08-12 | 美铝公司 | The 7XXX aluminium alloy improved and production method thereof |
WO2013172912A2 (en) * | 2012-03-07 | 2013-11-21 | Alcoa Inc. | Improved aluminum-lithium alloys, and methods for producing the same |
EP2822717A4 (en) * | 2012-03-07 | 2016-03-09 | Alcoa Inc | Improved 6xxx aluminum alloys, and methods for producing the same |
AU2013204114B2 (en) * | 2012-03-07 | 2016-04-14 | Arconic Inc. | Improved 2XXX aluminum alloys, and methods for producing the same |
AU2013205742B2 (en) * | 2012-03-07 | 2016-04-07 | Arconic Inc. | Improved 7XXX aluminium alloys, and methods for producing the same |
AU2013202789B2 (en) * | 2012-03-07 | 2016-04-21 | Arconic Inc. | Improved aluminum alloys containing magnesium, silicon, manganese, iron, and copper, and methods for producing same |
WO2013172910A2 (en) | 2012-03-07 | 2013-11-21 | Alcoa Inc. | Improved 2xxx aluminum alloys, and methods for producing the same |
DE102012209568B4 (en) | 2012-06-06 | 2016-01-14 | Technische Universität Bergakademie Freiberg | Method and device for casting rolls of magnesium wires |
US9587298B2 (en) * | 2013-02-19 | 2017-03-07 | Arconic Inc. | Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same |
CN114990389B (en) * | 2022-04-27 | 2023-06-16 | 永杰新材料股份有限公司 | Preparation method of aluminum alloy strip with hierarchical structure and aluminum alloy strip |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2693012A (en) * | 1950-09-08 | 1954-11-02 | Gen Motors Corp | Method and apparatus for manufacturing sheet material |
JPS6027450A (en) | 1983-07-26 | 1985-02-12 | Ishikawajima Harima Heavy Ind Co Ltd | Continuous casting method of steel plate |
US4751958A (en) * | 1985-10-04 | 1988-06-21 | Hunter Engineering Company, Inc. | Continuous casting aluminum alloy |
US4915158A (en) * | 1987-11-09 | 1990-04-10 | Hazelett Strip-Casting Corporation | Belt composition for improving performance and flatness of thin revolving endless flexible casting belts in continuous metal casting machines |
US5983980A (en) * | 1993-11-18 | 1999-11-16 | Isahikawajima-Harima Heavy Industries Co., Ltd. | Casting steel strip |
US5482107A (en) * | 1994-02-04 | 1996-01-09 | Inland Steel Company | Continuously cast electrical steel strip |
US5772799A (en) | 1995-09-18 | 1998-06-30 | Kaiser Aluminum & Chemical Corporation | Method for making can end and tab stock |
US5772802A (en) | 1995-10-02 | 1998-06-30 | Kaiser Aluminum & Chemical Corporation | Method for making can end and tab stock |
-
2003
- 2003-06-13 EP EP03737080.6A patent/EP1545812B1/en not_active Expired - Lifetime
- 2003-06-13 KR KR1020057002906A patent/KR101129489B1/en active IP Right Grant
- 2003-06-13 WO PCT/US2003/018764 patent/WO2004018124A1/en active Application Filing
- 2003-06-13 ES ES03737080T patent/ES2423825T3/en not_active Expired - Lifetime
- 2003-06-13 KR KR1020117004617A patent/KR20110026026A/en active IP Right Grant
- 2003-06-13 JP JP2004530797A patent/JP2005536354A/en active Pending
- 2003-06-13 AU AU2003236522A patent/AU2003236522A1/en not_active Abandoned
Also Published As
Publication number | Publication date |
---|---|
WO2004018124A1 (en) | 2004-03-04 |
ES2423825T3 (en) | 2013-09-24 |
AU2003236522A1 (en) | 2004-03-11 |
KR20110026026A (en) | 2011-03-14 |
KR20050058402A (en) | 2005-06-16 |
EP1545812A1 (en) | 2005-06-29 |
EP1545812A4 (en) | 2006-04-05 |
JP2005536354A (en) | 2005-12-02 |
KR101129489B1 (en) | 2012-03-28 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US7503378B2 (en) | Casting of non-ferrous metals | |
EP1545812B1 (en) | Casting of non-ferrous metals | |
EP1414602B1 (en) | Continuous casting of aluminum | |
US11008641B2 (en) | Corrosion resistant aluminum alloys having high amounts of magnesium and methods of making the same | |
US7846554B2 (en) | Functionally graded metal matrix composite sheet | |
US7125612B2 (en) | Casting of non-ferrous metals | |
CN1092343A (en) | Be used to produce the method for band steel, sheet billet or plate slab | |
US20130216426A1 (en) | Strip castings of immiscible metals | |
US5293926A (en) | Method and apparatus for direct casting of continuous metal strip | |
US7503377B2 (en) | Method and apparatus for continuous casting | |
US7089993B2 (en) | Method and apparatus for continuous casting | |
US6880617B2 (en) | Method and apparatus for continuous casting | |
Szczypiorski et al. | The mechanical and metallurgical characteristics of twin-belt cast aluminum strip using current Hazelett technology | |
KR20180091564A (en) | Non-ferrous metal casting | |
WO1995018876A1 (en) | Method and composition for castable aluminum alloys | |
Hammood et al. | forming technology to produce a very thin 5052 Al-alloy ribbon by direct casting from liquid state | |
Regan et al. | HISTORY OF DEVELOPMENT |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 20050225 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR |
|
AX | Request for extension of the european patent |
Extension state: AL LT LV MK |
|
DAX | Request for extension of the european patent (deleted) | ||
A4 | Supplementary search report drawn up and despatched |
Effective date: 20060216 |
|
17Q | First examination report despatched |
Effective date: 20070626 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R081 Ref document number: 60343943 Country of ref document: DE Owner name: ARCONIC INC., PITTSBURGH, US Free format text: FORMER OWNER: ALCOA INC., PITTSBURGH, PA., US |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP Ref country code: AT Ref legal event code: REF Ref document number: 609572 Country of ref document: AT Kind code of ref document: T Effective date: 20130515 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 60343943 Country of ref document: DE Effective date: 20130627 |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 609572 Country of ref document: AT Kind code of ref document: T Effective date: 20130501 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: T3 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2423825 Country of ref document: ES Kind code of ref document: T3 Effective date: 20130924 |
|
REG | Reference to a national code |
Ref country code: GR Ref legal event code: EP Ref document number: 20130401571 Country of ref document: GR Effective date: 20130829 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130902 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130801 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: CZ Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
26N | No opposition filed |
Effective date: 20140204 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20130613 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20130630 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20130630 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 60343943 Country of ref document: DE Effective date: 20140204 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20130501 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20130613 Ref country code: HU Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO Effective date: 20030613 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 14 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R081 Ref document number: 60343943 Country of ref document: DE Owner name: ARCONIC INC., PITTSBURGH, US Free format text: FORMER OWNER: ALCOA INC., PITTSBURGH, PA., US Ref country code: DE Ref legal event code: R081 Ref document number: 60343943 Country of ref document: DE Owner name: ARCONIC TECHNOLOGIES LLC, PITTSBURGH, US Free format text: FORMER OWNER: ALCOA INC., PITTSBURGH, PA., US Ref country code: DE Ref legal event code: R082 Ref document number: 60343943 Country of ref document: DE Representative=s name: BOEHMERT & BOEHMERT ANWALTSPARTNERSCHAFT MBB -, DE |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 15 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: CD Owner name: ARCONIC INC., US Effective date: 20170828 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: HC Owner name: ARCONIC INC.; US Free format text: DETAILS ASSIGNMENT: CHANGE OF OWNER(S), CHANGE OF OWNER(S) NAME; FORMER OWNER NAME: ALCOA INC. Effective date: 20171129 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 16 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: HC Owner name: ARCONIC INC.; US Free format text: DETAILS ASSIGNMENT: CHANGE OF OWNER(S), CHANGEMENT DE NOM DU PROPRIETAIRE; FORMER OWNER NAME: ALCOA INC. Effective date: 20180213 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: PC2A Owner name: ARCONIC INC. Effective date: 20190920 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 60343943 Country of ref document: DE Representative=s name: BOEHMERT & BOEHMERT ANWALTSPARTNERSCHAFT MBB -, DE Ref country code: DE Ref legal event code: R081 Ref document number: 60343943 Country of ref document: DE Owner name: ARCONIC TECHNOLOGIES LLC, PITTSBURGH, US Free format text: FORMER OWNER: ARCONIC INC., PITTSBURGH, PA., US |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: PC2A Owner name: ARCONIC TECHNOLOGIES LLC Effective date: 20200408 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: PD Owner name: ARCONIC TECHNOLOGIES LLC; US Free format text: DETAILS ASSIGNMENT: CHANGE OF OWNER(S), ASSIGNMENT; FORMER OWNER NAME: ARCONIC INC. Effective date: 20200403 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: PD Owner name: ARCONIC TECHNOLOGIES LLC; US Free format text: DETAILS ASSIGNMENT: CHANGE OF OWNER(S), CESSION Effective date: 20200408 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20200520 Year of fee payment: 18 Ref country code: DE Payment date: 20200519 Year of fee payment: 18 Ref country code: NL Payment date: 20200525 Year of fee payment: 18 Ref country code: GR Payment date: 20200525 Year of fee payment: 18 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IT Payment date: 20200519 Year of fee payment: 18 Ref country code: SE Payment date: 20200526 Year of fee payment: 18 Ref country code: GB Payment date: 20200525 Year of fee payment: 18 Ref country code: BE Payment date: 20200526 Year of fee payment: 18 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: 732E Free format text: REGISTERED BETWEEN 20200813 AND 20200819 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 20200701 Year of fee payment: 18 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R119 Ref document number: 60343943 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: EUG |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MM Effective date: 20210701 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20210613 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20210630 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210613 Ref country code: DE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20220101 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20220105 Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210630 Ref country code: SE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210614 Ref country code: NL Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210701 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210613 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210630 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20220803 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: ES Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210614 |