CA2410245A1 - Casting roll for a two-roll continuous casting installation - Google Patents
Casting roll for a two-roll continuous casting installation Download PDFInfo
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- CA2410245A1 CA2410245A1 CA002410245A CA2410245A CA2410245A1 CA 2410245 A1 CA2410245 A1 CA 2410245A1 CA 002410245 A CA002410245 A CA 002410245A CA 2410245 A CA2410245 A CA 2410245A CA 2410245 A1 CA2410245 A1 CA 2410245A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/06—Alloys based on copper with nickel or cobalt as the next major constituent
-
- 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
- B22D11/0637—Accessories therefor
- B22D11/0648—Casting surfaces
- B22D11/0651—Casting wheels
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
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- Mechanical Engineering (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Materials Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Continuous Casting (AREA)
- Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
- Extrusion Of Metal (AREA)
- Mold Materials And Core Materials (AREA)
- Rolls And Other Rotary Bodies (AREA)
Abstract
A casting roll of a two-roll continuous casting installation is to be able t o be exposed to a changing temperature stress and roll pressures when casting str ip made of non-ferrous metals, especially of aluminum or an aluminum alloy. For this purpose, its sleeve is made of an age-hardening copper alloy made of - as expressed in each case as weight % - 0.4 % through 2 % cobalt, which is partially exchangeable for nickel, 0.1 % through 0.5 % beryllium, optionally 0.03 % through. 0.5 % zirconium, 0.005 % through 0.1 % magnesium and possibly a maximum of 0.15 % of at least one element of the group including niobium, manganese, tantalum, vanadium, titanium, chromium, cerium and hafnium, the remainder being copper and inclusive of manufacturing- conditioned impurities and usual processing additives. H
Description
(364/96) CASTING ROLL FOR A~WO-ROLL COlVTLNUOUS CASTING INSTALLATION
B~1CKGR~)tIND pF THE INVENTION
Field of the Invention T'he invention relates to a casting roll for a two-roll continuous casting installation.
~escriDtion of Related Art The worldwide aim; especially of the steel industry, to pour semifinished product as close to final dimen lions as possible, in order to save hot and/or cold working steps, has led szn~;e about 1980 to a series of developments, such as single roll and two-roll continuous casting methods.
In these casting methods, very high surface temperatures appear at the «rater-cooled cylinders or rolls during casting of steel alloys, nickel, copper, as well as alloys that are only rolled with difficulty in the pouring range of the melt.
In the case of close to final dimension casting of a steel alloy, for example, the temperatures are about 350°C to 450°C, the sleeves of the continuous casting r olls being made of a CuCrZr rznaterial having an electrical conductivity of Sm/mm2 and a heat conductivity of about 320 W/mK. Materials based on ~~uCrZr were used up to nova predominantly for continuous casting dies and casting wheels than were trerrrzally hilly stressed. In the case of these materials, the surface temperature drops cyclically to about 150°C to 200°C, by the cooling of the casting rolls, with each revolution, shortly before the casting range. On the cooled rear side of the casting rolls, however, the temperature remains largely constant during the cycle, at about 30°C to 40°C. The temperature gradier~~. between the surface and the rear side in combination with th.e cyclical change in the surface temperature of the continuous casting rolls caust:a tW ermal Str~3S i1".'~ the surface region of the sleeve material.
525080v1 According to investigations of the fatigue properties of the CuCrZr materials used up to now, at various temperatures, using an expansion amplitude of +; - 0.3% and a frequency of 0.5 Hertz - these parameters approximately correspond to a rotational speed. caf the continuous casting rolls of 30 rpm. -one m.ay expect, for example, in the favorable case, a service life of 3000 cycles until cracks form, using a maximum surface temperature of 400°C, corresponding to a wall thickness of 25 mm above the water cooling. Therefore, the continuous casting rolls have to be reconditioned after as relatively early an operating time as about 100 minutes, for the purpose of removing surface cracks. In this context, the service life between reworking is, among other things, substantially dependent on the effectiveness of the lubrication j release agents at the casting surface, the constructive and process-conditioned cooling as well as the casting speed. For the purpose of exchanging the continuous casting rolls, the casting installation has to be stopped and the casting process has to be interrupted.
A further disadvantage of the proven mold material CuCrZr for this particular application is the relatively low hardness of approximately 110 HBW to 130 1IBW. For, in the case of a cinglc: roll or two-roll continuous casting method, it is not to be avoided that, even before the casting range, splashes appear on the roll surfaces. The solidified steel particles are then pressed into the relatively soft surfaces of the continuous casting rolls, whereby the surface quality of the poured strips of about 1.5 mm to 4 mm thickness are considerably impaired.
Compared to a CuCz~'?r alloy, the lower electrical conductivity of a known C:uNiBe alloy, haring an additi~::~.r.~ ~.~f tan to 1% niobium, also leads to a higher ~;urface temperature. SiY~ce tht:; electrical conductivity behaves approximately proportionally to the heat condu~ctivi~cy, the surfar_e temperature in the sleeve, of a continuous casting roll, rnad~: of the CuNiBe alloy as composed to a continuous casting roll having a sleeve made of CuCrZr, at a maximum temperature of 400°C at the surface and 30°C on the rear side will be increased to about 540°C.
:~iso8o~i 2 Ternary CuNiBe and CuCoBe alloys do indeed basically demonstrate a Brinell hardness of more than 200 HBW, however, the electrical conductivity of the standard semifinished pxoducts made of these materials, such as rod for manufacturing resistance welding electrodes or sheet or strip for manufacturing springs or Ieadframes, reach values of at most in the range of 26 Sm/mma to about 32 Sm/ man2. Ur_der npti~~num conditions, with the use of these standard materials, a surface temperature of only about 585°C could be reached at the sleeve of a continuous casting roll.
Even from the CuCoBeZr and CuNiBeZr alloys basically known from U. S. Patent No. 4,179,314, no hints are seem that conductivity values of > 38 Sm/mm2 in conjunction with a minimum hardness of 200 HBW could be achieved.
Within the scope of EP 0 5~+~3 63Ei B I , the use of an age-hardening copper ahoy is also related art, which has 1.0% to 2.6 % nickel that rnay be fully or partially replaced by cobalt, 0.1 aIo to 0,~5 ~'~o beryllium, optionally 0.05 % to 0.25 %.
zirconium and possibly up to a maximum of 0.15 % of at least one of the group of elements including niobium, tantalum, vanadium, titanium, chromium, cerium and hafnium, the rest being copper inclusive of production-conditioned c:ontaminations and usual proc::essing additives, having a $rinell hardness of at least 200 HBW and an electrical conductivity greater than 38 Sm/mm~ as the material for producing continuous casting rolls and wheels.
Alloys having these compositions, such as the alloys CuCo2Be0.5 or CuNi28e0.5, have disadvantages in their hot forming capability, because of their relatively high alloying elernent content. However, high heat deformation strains are required to attain :a, f re grained product having a grain size <
1.5 xnm (as per ASTM E 1 I2}, starting from a coarse-grained cast structure having a grain size of several millimeter's. In particular, far large format casting rolls, up to this point, sufficiently large continuous casting rolls have been producible only at very high expenditure; however, technical shaping devices are hardly available for realizing, at a justifiable cost, a sufficiently high hot kneading for 525080v1 3 recrystallization of the cast structure into a fine grain structure.
SUMM~1~:Y OF THE INVENTION
It is an object of the invention to create a continuous casting roll as a component of a two-roll contin~.~o-us casting installation, which, during close to final dimension casting of strips made of non-ferrous metals, may be exposed without any problem to changing temperature stresses and high roll pressures, while having a long service life.
These and other objects of the invention are attained by a casting roll for a two-roll continuous casting insla?lation, which has a sleeve made of an age-hardening copper alloy made of - as expressed in each case as weight % -0.4 % through 2 % cobalt, which is partially exchangeable for nickel, 0, I
through 0.5 % beryllium, optionally 0,03 % through 0.5 % zirconium, 0.005 through 0.1 % magnesium and. possibly a maximum of 0.15 % of at least one element of the gz-oup including niobium, manganese, tantalum, vanadium, titanium, chromium, cer ium, and hafnium, the remainder being copper inclusive of manufacturing-conditioned irnpurities and usual processing additives.
During the casting of strips made of non-ferrous metals, the casting roll may undexgo changing temperature stress and high roll pressures, DETAILED DESCRIPTION OF THE INVENTION
I3y the use of a CuCoBe2r(Mg) alloy having an intentionally graded low content of Co and Be, on the one hand, one may ensure a still sufficient age-hardenability of the rnateria.l for achieving high strength, hardness and c~onductavity; on the other hand, only low heat deformation strain is required for the complete recrystalli2ation of the cast structure and the setting of a ;fine-grained structure having sufficient ductility.
Due to a continuous casting roll thus developed as a component of a two-roll continuous casting installatiorn, it is possible to increase the casting speed of a strip made of a non-ferrous metal, particularly of aluminum or an aluminum 52S080v1 4 a.:lloy, by more than double, cor~vp;~red to a roll installation in which the rolls are fitted with steel sleeves. In add:iti:~7n, a clearly improved surface quality of the cast strip is achieved. Also, a considerably longer service life is ensured for the s;;eeve.
This continuous casting roll may 5e developed as a hollow cylinder, i.e.
inherently rigid without a core. '1'he surface coming into contact with, the strips to be cast, however, may also be a component of a sleeve having a core, especially a steel core. The sleeve°_ may then be shrink fitted onto such a core as the earner, hot isostatically pres<,aed on or slipped on and then locked mechanically.
Ii: is also conceivable, when using a sleeve, that this could be developed as a single layer or multiple layers.
The enveloping surface of the sur:°ace of the casting roll may be designed cylindrically or having a camber, so as possibly to compensate for the sagging of a roll, A, further improvement ir_ the sle~ewe's mechanical properties, particularly an increase in tensile strength, may be advantageously achieved, if the copper alloy contains 0.03 % to U.35 % zirccan.iurr~, and 0.005 % to 0.05 % magnesium.
According to a further specific en~.bodiment, the copper alloy contains a proportion < 1.0 % of cobalt, 0. :LS % to 0,3 % of beryllium and 0.15 % to 0.3 % of zirconium.
I~t is also of advantage if the ratio of cobalt to beryllium in the copper alloy of the sleeve is between 2 and i 5. M~:>s2 preferably, This ratio of cobalt to beryllium is
B~1CKGR~)tIND pF THE INVENTION
Field of the Invention T'he invention relates to a casting roll for a two-roll continuous casting installation.
~escriDtion of Related Art The worldwide aim; especially of the steel industry, to pour semifinished product as close to final dimen lions as possible, in order to save hot and/or cold working steps, has led szn~;e about 1980 to a series of developments, such as single roll and two-roll continuous casting methods.
In these casting methods, very high surface temperatures appear at the «rater-cooled cylinders or rolls during casting of steel alloys, nickel, copper, as well as alloys that are only rolled with difficulty in the pouring range of the melt.
In the case of close to final dimension casting of a steel alloy, for example, the temperatures are about 350°C to 450°C, the sleeves of the continuous casting r olls being made of a CuCrZr rznaterial having an electrical conductivity of Sm/mm2 and a heat conductivity of about 320 W/mK. Materials based on ~~uCrZr were used up to nova predominantly for continuous casting dies and casting wheels than were trerrrzally hilly stressed. In the case of these materials, the surface temperature drops cyclically to about 150°C to 200°C, by the cooling of the casting rolls, with each revolution, shortly before the casting range. On the cooled rear side of the casting rolls, however, the temperature remains largely constant during the cycle, at about 30°C to 40°C. The temperature gradier~~. between the surface and the rear side in combination with th.e cyclical change in the surface temperature of the continuous casting rolls caust:a tW ermal Str~3S i1".'~ the surface region of the sleeve material.
525080v1 According to investigations of the fatigue properties of the CuCrZr materials used up to now, at various temperatures, using an expansion amplitude of +; - 0.3% and a frequency of 0.5 Hertz - these parameters approximately correspond to a rotational speed. caf the continuous casting rolls of 30 rpm. -one m.ay expect, for example, in the favorable case, a service life of 3000 cycles until cracks form, using a maximum surface temperature of 400°C, corresponding to a wall thickness of 25 mm above the water cooling. Therefore, the continuous casting rolls have to be reconditioned after as relatively early an operating time as about 100 minutes, for the purpose of removing surface cracks. In this context, the service life between reworking is, among other things, substantially dependent on the effectiveness of the lubrication j release agents at the casting surface, the constructive and process-conditioned cooling as well as the casting speed. For the purpose of exchanging the continuous casting rolls, the casting installation has to be stopped and the casting process has to be interrupted.
A further disadvantage of the proven mold material CuCrZr for this particular application is the relatively low hardness of approximately 110 HBW to 130 1IBW. For, in the case of a cinglc: roll or two-roll continuous casting method, it is not to be avoided that, even before the casting range, splashes appear on the roll surfaces. The solidified steel particles are then pressed into the relatively soft surfaces of the continuous casting rolls, whereby the surface quality of the poured strips of about 1.5 mm to 4 mm thickness are considerably impaired.
Compared to a CuCz~'?r alloy, the lower electrical conductivity of a known C:uNiBe alloy, haring an additi~::~.r.~ ~.~f tan to 1% niobium, also leads to a higher ~;urface temperature. SiY~ce tht:; electrical conductivity behaves approximately proportionally to the heat condu~ctivi~cy, the surfar_e temperature in the sleeve, of a continuous casting roll, rnad~: of the CuNiBe alloy as composed to a continuous casting roll having a sleeve made of CuCrZr, at a maximum temperature of 400°C at the surface and 30°C on the rear side will be increased to about 540°C.
:~iso8o~i 2 Ternary CuNiBe and CuCoBe alloys do indeed basically demonstrate a Brinell hardness of more than 200 HBW, however, the electrical conductivity of the standard semifinished pxoducts made of these materials, such as rod for manufacturing resistance welding electrodes or sheet or strip for manufacturing springs or Ieadframes, reach values of at most in the range of 26 Sm/mma to about 32 Sm/ man2. Ur_der npti~~num conditions, with the use of these standard materials, a surface temperature of only about 585°C could be reached at the sleeve of a continuous casting roll.
Even from the CuCoBeZr and CuNiBeZr alloys basically known from U. S. Patent No. 4,179,314, no hints are seem that conductivity values of > 38 Sm/mm2 in conjunction with a minimum hardness of 200 HBW could be achieved.
Within the scope of EP 0 5~+~3 63Ei B I , the use of an age-hardening copper ahoy is also related art, which has 1.0% to 2.6 % nickel that rnay be fully or partially replaced by cobalt, 0.1 aIo to 0,~5 ~'~o beryllium, optionally 0.05 % to 0.25 %.
zirconium and possibly up to a maximum of 0.15 % of at least one of the group of elements including niobium, tantalum, vanadium, titanium, chromium, cerium and hafnium, the rest being copper inclusive of production-conditioned c:ontaminations and usual proc::essing additives, having a $rinell hardness of at least 200 HBW and an electrical conductivity greater than 38 Sm/mm~ as the material for producing continuous casting rolls and wheels.
Alloys having these compositions, such as the alloys CuCo2Be0.5 or CuNi28e0.5, have disadvantages in their hot forming capability, because of their relatively high alloying elernent content. However, high heat deformation strains are required to attain :a, f re grained product having a grain size <
1.5 xnm (as per ASTM E 1 I2}, starting from a coarse-grained cast structure having a grain size of several millimeter's. In particular, far large format casting rolls, up to this point, sufficiently large continuous casting rolls have been producible only at very high expenditure; however, technical shaping devices are hardly available for realizing, at a justifiable cost, a sufficiently high hot kneading for 525080v1 3 recrystallization of the cast structure into a fine grain structure.
SUMM~1~:Y OF THE INVENTION
It is an object of the invention to create a continuous casting roll as a component of a two-roll contin~.~o-us casting installation, which, during close to final dimension casting of strips made of non-ferrous metals, may be exposed without any problem to changing temperature stresses and high roll pressures, while having a long service life.
These and other objects of the invention are attained by a casting roll for a two-roll continuous casting insla?lation, which has a sleeve made of an age-hardening copper alloy made of - as expressed in each case as weight % -0.4 % through 2 % cobalt, which is partially exchangeable for nickel, 0, I
through 0.5 % beryllium, optionally 0,03 % through 0.5 % zirconium, 0.005 through 0.1 % magnesium and. possibly a maximum of 0.15 % of at least one element of the gz-oup including niobium, manganese, tantalum, vanadium, titanium, chromium, cer ium, and hafnium, the remainder being copper inclusive of manufacturing-conditioned irnpurities and usual processing additives.
During the casting of strips made of non-ferrous metals, the casting roll may undexgo changing temperature stress and high roll pressures, DETAILED DESCRIPTION OF THE INVENTION
I3y the use of a CuCoBe2r(Mg) alloy having an intentionally graded low content of Co and Be, on the one hand, one may ensure a still sufficient age-hardenability of the rnateria.l for achieving high strength, hardness and c~onductavity; on the other hand, only low heat deformation strain is required for the complete recrystalli2ation of the cast structure and the setting of a ;fine-grained structure having sufficient ductility.
Due to a continuous casting roll thus developed as a component of a two-roll continuous casting installatiorn, it is possible to increase the casting speed of a strip made of a non-ferrous metal, particularly of aluminum or an aluminum 52S080v1 4 a.:lloy, by more than double, cor~vp;~red to a roll installation in which the rolls are fitted with steel sleeves. In add:iti:~7n, a clearly improved surface quality of the cast strip is achieved. Also, a considerably longer service life is ensured for the s;;eeve.
This continuous casting roll may 5e developed as a hollow cylinder, i.e.
inherently rigid without a core. '1'he surface coming into contact with, the strips to be cast, however, may also be a component of a sleeve having a core, especially a steel core. The sleeve°_ may then be shrink fitted onto such a core as the earner, hot isostatically pres<,aed on or slipped on and then locked mechanically.
Ii: is also conceivable, when using a sleeve, that this could be developed as a single layer or multiple layers.
The enveloping surface of the sur:°ace of the casting roll may be designed cylindrically or having a camber, so as possibly to compensate for the sagging of a roll, A, further improvement ir_ the sle~ewe's mechanical properties, particularly an increase in tensile strength, may be advantageously achieved, if the copper alloy contains 0.03 % to U.35 % zirccan.iurr~, and 0.005 % to 0.05 % magnesium.
According to a further specific en~.bodiment, the copper alloy contains a proportion < 1.0 % of cobalt, 0. :LS % to 0,3 % of beryllium and 0.15 % to 0.3 % of zirconium.
I~t is also of advantage if the ratio of cobalt to beryllium in the copper alloy of the sleeve is between 2 and i 5. M~:>s2 preferably, This ratio of cobalt to beryllium is
2.2 to 5.
?'he invention permits having they copper alloy contain, in addition to cobalt, up s2so8om 5 to 0.6 % nickel.
Further improvements of the xnec:hanical properties of the casting roll may be achieved if the copper alloy of the sleeve contains up to a maximum of 0.15 %
of at least one element of the group including niobium, manganese, tantalum, vanadium, titanium, chromium, cerium and hafnium_ The sleeve is advantageously produced by the processing steps casting, hot working, solufiion treatment at 850°C to 98U°C, cold working up to 30 % as well as age-hardening at 400°C to 550°C within a period of 4 to 32 hours, the sleeve having a maximum average gain size of 1, 5 mm as per ASTM E 1 I2, a hardness of at least 170 HBW, and an electrical conductivity of at least 26 Sm/mm2.
> It: is of particular advantage if th~; sleeve in the age-hardened state, has an average grain size of 30 darn to ;IOU ~.m as per ASTM E 112, a hardness of at least 185 HBW, a conductivity between 30 and 36 Sm/ mm=, a 0.2 % yield strength of at least 450 MPa and an elongation at break of at least 12 %.
If the sleeve is provided with a coating which reduces the permeability to heat, or evens out the flow of heat, the product quality of the cast strip made of a non-ferrous metal, but particularly of aluminum or an aluminum alloy, is further enhanced. Based ors tlae operating condition of the sleeve, this coating, specifically made of a copper alloy, is made effective, especially in the case of an aluminum strip, d~:e to the fac~f: that, at the beginning of a casting or rolling process, an adhesion layer form:; from the acting together of copper and aluminum on the surface of the sleeve, from which, then, during the further course of the casting process a'lu.minum penetrates the copper surface and there forms a stable, resistive diffusion layer, whose thickness and properties are essentially deternr~ined b~.~ the casting speed and cooling conditions.
That clearly improves the su.~-face qua.lit~~ of the aluminum strip and consequently the product quality.
sasosori 6 The service life of the sleeve carp be prolonged even further by using a coating having a great surface hardness.
The surface of the casting roll may be made smooth. This design is achievable l particularly by rolling. In this xna.nner, pressure stresses are induced in the edge zone, and these make possible additional resistance to the formation of cracks and the progression of cracks, so as to raise the life duration of the casting roll.
The surface of the casting roll tray be textured. Texturing can be applied, for example, by cutting, roller-bur~~ishing, eroding or blasting. With the use of such measures, the heat transfer coefficient may specifically be influenced, I:~. the depressions formed by flue texturing, a substance may be embedded l having a low heat evnductivity compared to the heat conductivity of copper.
Ftesides being a metallic materaal, such as particularly nickel or a nickel alloy, such a substance rrday also be a ceramic material. Such a filling up of the depressions formed by the textwring on the surface of the casting roll is used to create good surface quality and to ensure a lasting influence on the heat conductivity.
T'he invention is explained in greater detail with reference to the examples t~elow. In the light of s~v~en alhays for the sleeve of a casting roll (alloys A to G) a.nd three comparison alloys (H to J), it is shown how critical the composition is to achieving the combinations ~af properties aimed for.
P,11 the alloys were smelted in a crucible furnace and cast into round billets of equal format. The composition of the individual layers is given below in Table 1.
T'he addition of magnesium is made for the pre-deoxidization of the melt, and t:he addition of zirconium acts positively on the hot ductility.
S:Z5080v 1 7 ble 1 f~lloy Co(%1 Ni(%) Be(%1__ Zr(/gl Mg,(,%~ Cuj%) A 0.68 - 0.20 0.20 0.03 Rest B 1.0 - 0.22 0.22 0.03 Rest t: 1.4 - fi~.20 0.18 0.02 Rest D 0.65 - 0.29 0.21 0.04 Rest F: 1.0 - 0.31 0.24 0.01 Rest 1.4 - 0.28 0.19 0.03 Rest (s 1.0 0.1 0.22 0.16 0.03 Rest H - 1,7 0.27 0.16 - Rest :l 2.1 - 0.55 0.24 - Rest ~T - 1.4 0.54 0.20 - Rest The alloys Were subseduently ~r~°ssed into flat bars using a low pressure ratio (= cross section of the cast blot:k; j cross section of the pressed bar) of 5,6:1 on an e~.xtrusion press at 950°C. Thereafter, the alloys were submitted to an at least 30-minute solution treatment above 850°C, using a subsequent water quenching, and after that, were age-hardened for 4 to 32 hours at a t:emperature range 'between 400"C and 550°C. The combinations of properties attained are shown in Table 2 bc;low.
able 2 Alloy Rm Rp°,a A HBW 2,5 El.Cond. Grain Size MPa MPa % .187.5 Srn/rnma mm A 694 492 21 <;C)7 36.8 0.09 - 0.25 B 675 4$6 18 ~07 32.8 0.09 - 0.18 C 651 495 18 2 3.1 30.0 0.045- 0.13 I~ 707 501 19 207 31.4 0.09 - 0.25 E 735 505 19 229 33.6 0.045- 0.18 5~z5080v1 8 F 735 520 19 224 32.3 0.09 - 0.25 G 696 513 18 :z :13 33 , 5 0.065- 0.18 H 688 556 10 202 41.0 2-3 i 1 784 S41 11 2;~9 :30.3 1.5-3 J 645 510 4 198 30.9 4-6 &:m = tensile strength p~Po.a = 0.2 % yield strength A. = elongation at break HBW = Brinell hardness A,s may be seen from the combinations of properties, the alloys according to the present invention, for producing a sleeve of a casting roll, attain the aimed-for i recrystalli2ed fine grained struc:2ure while having an appropriately good elongation at break. In the cage of comparison alloys H to J, there is a grain .
size of more than i.5 mm, which reduces the ductility of the material.
P.~n additional increase in strength may be attained by cold forming before the a.ge-hardening. Table 3 below eves the property combinations of alloys A to J, v~rhich are achieved by solution treatment of the pressed material for at least 30 nninutes above 850 °c and subsequent water quenching, 10 % to 15 % cold rolling (reduction in cross section) and then age-hardening from 2 to 32 hours a.t a temperature range betmeea~ 400°C and 550°C.
i able 3 Alloy Rm Rpo,2 A :HBW 2,5 El,Cond. Grain Size MPa MPa % :LF~7.5 Sm,/mm2 mrn A, 688 532 20 :~ l.1 36.7 0.13 - 0.25 1=t 679 534 18 ~C37 34 6 0.045- 0.18 ~zsosoY~ 9 C: 741 60.0 17 ~?2~,7 34.4 0.065- 0.18 L7 690 537 21 207 32.6 0.065- 0.25 E; 735 576 19 ~?3~0 ;34.7 0.045- 0.18 F 741 600 17 227 34.4 0.13 - 0,25 i G 695 591 15 ~?2,4 33.0 0.18 - 0.35 1-t 75I 689 9 :302 40.9 2-4 1 836 712. i0 229 31.0 2-3 1 726 651 6 :1.98 31.5 3-6 Alloys A to G according to the preaent invention, in turn, demonstrate good elongations at break and a grain size less than 0.5 mm, while comparison alloys I-'f to J have a coarse grain, hav:~ng a grain size greater than 1.5 mm and lower values of elongation at break. Thus, these copper alloys have clear processing advantages during the producti.o» of sleeves, particularly for larger continuous casting rolls of two-roll casting .installations, whereby it is made possible to produce a fine grained end product having optimum basic properties fox their field of application, saso8om 10
?'he invention permits having they copper alloy contain, in addition to cobalt, up s2so8om 5 to 0.6 % nickel.
Further improvements of the xnec:hanical properties of the casting roll may be achieved if the copper alloy of the sleeve contains up to a maximum of 0.15 %
of at least one element of the group including niobium, manganese, tantalum, vanadium, titanium, chromium, cerium and hafnium_ The sleeve is advantageously produced by the processing steps casting, hot working, solufiion treatment at 850°C to 98U°C, cold working up to 30 % as well as age-hardening at 400°C to 550°C within a period of 4 to 32 hours, the sleeve having a maximum average gain size of 1, 5 mm as per ASTM E 1 I2, a hardness of at least 170 HBW, and an electrical conductivity of at least 26 Sm/mm2.
> It: is of particular advantage if th~; sleeve in the age-hardened state, has an average grain size of 30 darn to ;IOU ~.m as per ASTM E 112, a hardness of at least 185 HBW, a conductivity between 30 and 36 Sm/ mm=, a 0.2 % yield strength of at least 450 MPa and an elongation at break of at least 12 %.
If the sleeve is provided with a coating which reduces the permeability to heat, or evens out the flow of heat, the product quality of the cast strip made of a non-ferrous metal, but particularly of aluminum or an aluminum alloy, is further enhanced. Based ors tlae operating condition of the sleeve, this coating, specifically made of a copper alloy, is made effective, especially in the case of an aluminum strip, d~:e to the fac~f: that, at the beginning of a casting or rolling process, an adhesion layer form:; from the acting together of copper and aluminum on the surface of the sleeve, from which, then, during the further course of the casting process a'lu.minum penetrates the copper surface and there forms a stable, resistive diffusion layer, whose thickness and properties are essentially deternr~ined b~.~ the casting speed and cooling conditions.
That clearly improves the su.~-face qua.lit~~ of the aluminum strip and consequently the product quality.
sasosori 6 The service life of the sleeve carp be prolonged even further by using a coating having a great surface hardness.
The surface of the casting roll may be made smooth. This design is achievable l particularly by rolling. In this xna.nner, pressure stresses are induced in the edge zone, and these make possible additional resistance to the formation of cracks and the progression of cracks, so as to raise the life duration of the casting roll.
The surface of the casting roll tray be textured. Texturing can be applied, for example, by cutting, roller-bur~~ishing, eroding or blasting. With the use of such measures, the heat transfer coefficient may specifically be influenced, I:~. the depressions formed by flue texturing, a substance may be embedded l having a low heat evnductivity compared to the heat conductivity of copper.
Ftesides being a metallic materaal, such as particularly nickel or a nickel alloy, such a substance rrday also be a ceramic material. Such a filling up of the depressions formed by the textwring on the surface of the casting roll is used to create good surface quality and to ensure a lasting influence on the heat conductivity.
T'he invention is explained in greater detail with reference to the examples t~elow. In the light of s~v~en alhays for the sleeve of a casting roll (alloys A to G) a.nd three comparison alloys (H to J), it is shown how critical the composition is to achieving the combinations ~af properties aimed for.
P,11 the alloys were smelted in a crucible furnace and cast into round billets of equal format. The composition of the individual layers is given below in Table 1.
T'he addition of magnesium is made for the pre-deoxidization of the melt, and t:he addition of zirconium acts positively on the hot ductility.
S:Z5080v 1 7 ble 1 f~lloy Co(%1 Ni(%) Be(%1__ Zr(/gl Mg,(,%~ Cuj%) A 0.68 - 0.20 0.20 0.03 Rest B 1.0 - 0.22 0.22 0.03 Rest t: 1.4 - fi~.20 0.18 0.02 Rest D 0.65 - 0.29 0.21 0.04 Rest F: 1.0 - 0.31 0.24 0.01 Rest 1.4 - 0.28 0.19 0.03 Rest (s 1.0 0.1 0.22 0.16 0.03 Rest H - 1,7 0.27 0.16 - Rest :l 2.1 - 0.55 0.24 - Rest ~T - 1.4 0.54 0.20 - Rest The alloys Were subseduently ~r~°ssed into flat bars using a low pressure ratio (= cross section of the cast blot:k; j cross section of the pressed bar) of 5,6:1 on an e~.xtrusion press at 950°C. Thereafter, the alloys were submitted to an at least 30-minute solution treatment above 850°C, using a subsequent water quenching, and after that, were age-hardened for 4 to 32 hours at a t:emperature range 'between 400"C and 550°C. The combinations of properties attained are shown in Table 2 bc;low.
able 2 Alloy Rm Rp°,a A HBW 2,5 El.Cond. Grain Size MPa MPa % .187.5 Srn/rnma mm A 694 492 21 <;C)7 36.8 0.09 - 0.25 B 675 4$6 18 ~07 32.8 0.09 - 0.18 C 651 495 18 2 3.1 30.0 0.045- 0.13 I~ 707 501 19 207 31.4 0.09 - 0.25 E 735 505 19 229 33.6 0.045- 0.18 5~z5080v1 8 F 735 520 19 224 32.3 0.09 - 0.25 G 696 513 18 :z :13 33 , 5 0.065- 0.18 H 688 556 10 202 41.0 2-3 i 1 784 S41 11 2;~9 :30.3 1.5-3 J 645 510 4 198 30.9 4-6 &:m = tensile strength p~Po.a = 0.2 % yield strength A. = elongation at break HBW = Brinell hardness A,s may be seen from the combinations of properties, the alloys according to the present invention, for producing a sleeve of a casting roll, attain the aimed-for i recrystalli2ed fine grained struc:2ure while having an appropriately good elongation at break. In the cage of comparison alloys H to J, there is a grain .
size of more than i.5 mm, which reduces the ductility of the material.
P.~n additional increase in strength may be attained by cold forming before the a.ge-hardening. Table 3 below eves the property combinations of alloys A to J, v~rhich are achieved by solution treatment of the pressed material for at least 30 nninutes above 850 °c and subsequent water quenching, 10 % to 15 % cold rolling (reduction in cross section) and then age-hardening from 2 to 32 hours a.t a temperature range betmeea~ 400°C and 550°C.
i able 3 Alloy Rm Rpo,2 A :HBW 2,5 El,Cond. Grain Size MPa MPa % :LF~7.5 Sm,/mm2 mrn A, 688 532 20 :~ l.1 36.7 0.13 - 0.25 1=t 679 534 18 ~C37 34 6 0.045- 0.18 ~zsosoY~ 9 C: 741 60.0 17 ~?2~,7 34.4 0.065- 0.18 L7 690 537 21 207 32.6 0.065- 0.25 E; 735 576 19 ~?3~0 ;34.7 0.045- 0.18 F 741 600 17 227 34.4 0.13 - 0,25 i G 695 591 15 ~?2,4 33.0 0.18 - 0.35 1-t 75I 689 9 :302 40.9 2-4 1 836 712. i0 229 31.0 2-3 1 726 651 6 :1.98 31.5 3-6 Alloys A to G according to the preaent invention, in turn, demonstrate good elongations at break and a grain size less than 0.5 mm, while comparison alloys I-'f to J have a coarse grain, hav:~ng a grain size greater than 1.5 mm and lower values of elongation at break. Thus, these copper alloys have clear processing advantages during the producti.o» of sleeves, particularly for larger continuous casting rolls of two-roll casting .installations, whereby it is made possible to produce a fine grained end product having optimum basic properties fox their field of application, saso8om 10
Claims (19)
1. A casting roll for a two-roll continuous casting installation which, during the casting of strips made of non-ferrous metals, undergoes changing temperature stress and high roll pressures, comprising a sleeve made of an age-hardening copper ahoy, which includes in weight %: 0.4 % through 2 %
cobalt, which may be partially substituted with nickel, 0.1 % through 0.5%
beryllium, and a remainder of copper.
cobalt, which may be partially substituted with nickel, 0.1 % through 0.5%
beryllium, and a remainder of copper.
2. The casting roll according to Claim 1, in which the copper alloy further includes 0.03% through 0.5% zirconium and 0.005% through 0.1% magnesium.
3. The casting roll according to Claim 1, in which the copper alloy further includes a maximum of 0.15 % of at least one element selected from the group consisting of niobium, manganese, tantalum, vanadium, titanium, chromium, cerium and hafnium,
4. The casting roll according to Claim 2, in which the copper alloy contains 0.03 % to 0.35 % zirconium and 0.005 % to 0.05 % magnesium.
5. The casting roll according to Claim 2, in which the copper alloy contains less than 1.0 % cobalt, 0.15 % through 0.3 % beryllium and 0.15 % through 0.3 % of zirconium,
6. The casting roll according to Claim 1, in which the copper alloy has a ratio of cobalt to beryllium of between 2 and 15.
7. The casting roll according to Claim 2, in which the copper alloy has a ratio of cobalt to beryllium of between 2 and 15.
8. The casting roll according to Claim 3, in which the copper alloy has a ratio of cobalt to beryllium of between 2 and 15.
9. The casting roll according to Claim 6, in which the copper alloy has a ratio of cobalt to beryllium of between 2,2 and 5.
10. The casting roll according to Claim 1, in which the copper alloy further includes up to 0.6 % nickel in addition to cobalt.
11. The casting roll according to Claim 2, in which the copper alloy further includes up to 0.6 % nickel in addition to cobalt
12. The casting roll according to Claim 2, in which the copper alloy further includes a maximum of 0.15 % of at least one element selected from the group consisting of niobium, manganese, tantalum, vanadium, titanium, chromium, cerium and hafnium.
13. The casting roll according to Claim 1, wherein the sleeve is produced by casting, hot working, solution treatment at 850°C to 980°C, cold working up to 30 % as well as age-hardening at 400°C to 550°C within a time period of 4 to 32 hours, the sleeve having a maximum average grain size of 1.5 mm as per ASTM E 112, a hardness of at least 170 HBW, and an electrical conductivity of at least 26 Sm/ mm2.
14. The casting roll according to Claim 13, in which the sleeve, in the age-hardened state, has an average grain size of 30 µm to 500 µm as per ASTM
E 112, a hardness of at least 185 HBW, a conductivity between 30 and 36 Sm/mm2, a 0.2 % yield strength of at least 450 MPa and an elongation at break of at least 12 %.
E 112, a hardness of at least 185 HBW, a conductivity between 30 and 36 Sm/mm2, a 0.2 % yield strength of at least 450 MPa and an elongation at break of at least 12 %.
15. The casting roll according to Claim 1, in which the sleeve is provided with a coating that reduces the permeability to heat.
16. The casting roll according to Claim 15, in which the coating has a great surface hardness.
17. The casting roll according to Claim 1, in which the surface is designed to be smooth.
18. The casting roll according to Claim 1, in which the surface is textured.
19. The casting roll according to Claim 18, in which a substance is embedded in the depressions, formed by the texturing, which has a low heat conductivity compared to the heat conductivity of copper.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE10156926.2 | 2001-11-21 | ||
| DE10156926 | 2001-11-21 | ||
| DE10224268A DE10224268A1 (en) | 2001-11-21 | 2002-05-31 | Casting roll for a two-roll casting plant |
| DE10224268.2 | 2002-05-31 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2410245A1 true CA2410245A1 (en) | 2003-05-21 |
| CA2410245C CA2410245C (en) | 2017-03-21 |
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ID=26010619
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2410245A Expired - Lifetime CA2410245C (en) | 2001-11-21 | 2002-10-28 | Casting roll for a two-roll continuous casting installation |
Country Status (10)
| Country | Link |
|---|---|
| US (1) | US20030094219A1 (en) |
| EP (1) | EP1314495B1 (en) |
| JP (1) | JP4295492B2 (en) |
| KR (1) | KR100961239B1 (en) |
| CN (1) | CN1419982A (en) |
| BR (1) | BR0204713A (en) |
| CA (1) | CA2410245C (en) |
| MX (1) | MXPA02010879A (en) |
| NO (1) | NO340437B1 (en) |
| TW (1) | TW590822B (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE502004005671D1 (en) * | 2003-12-01 | 2008-01-17 | Sms Demag Ag | HASPEL DRIVER WITH DRIVER ROLLERS WITH MOLDINGS |
| CN101333609B (en) * | 2007-06-28 | 2011-03-16 | 周水军 | Low copper beryllium mold material for gravitation and low-pressure casting and production process thereof |
| DE102008015096A1 (en) * | 2008-03-19 | 2009-09-24 | Kme Germany Ag & Co. Kg | Process for producing molded parts and molded parts produced by the process |
| DE102019214056A1 (en) | 2019-09-16 | 2021-03-18 | Aktiebolaget Skf | ROLL COVER, ROLL BODY AND PROCESS |
| CN113234956B (en) * | 2021-05-14 | 2022-05-24 | 中铝沈阳有色金属加工有限公司 | Vacuum casting method for large-tonnage chromium-zirconium-copper cast ingot |
Family Cites Families (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3830644A (en) * | 1969-09-19 | 1974-08-20 | Hitachi Shipbuilding Eng Co | Copper alloy for plastic-working molds |
| US4179314A (en) * | 1978-12-11 | 1979-12-18 | Kawecki Berylco Industries, Inc. | Treatment of beryllium-copper alloy and articles made therefrom |
| US4377424A (en) * | 1980-05-26 | 1983-03-22 | Chuetsu Metal Works Co., Ltd. | Mold of precipitation hardenable copper alloy for continuous casting mold |
| US4657601A (en) * | 1983-11-10 | 1987-04-14 | Brush Wellman Inc. | Thermomechanical processing of beryllium-copper alloys |
| US4599120A (en) * | 1985-02-25 | 1986-07-08 | Brush Wellman Inc. | Processing of copper alloys |
| JPS6260879A (en) * | 1985-09-10 | 1987-03-17 | Ngk Insulators Ltd | Wear resistant copper alloy member |
| JPH02111835A (en) * | 1988-10-20 | 1990-04-24 | Chuetsu Gokin Chuko Kk | Mold material for electromagnetic stirring |
| JP2869076B2 (en) * | 1988-12-19 | 1999-03-10 | 中越合金鋳工株式会社 | Precipitation hardening mold material for continuous casting |
| DE4142941A1 (en) * | 1991-12-24 | 1993-07-01 | Kabelmetal Ag | USE OF A CURABLE copper alloy |
| JP3303623B2 (en) * | 1995-09-22 | 2002-07-22 | 三菱マテリアル株式会社 | Method for producing copper alloy mold material for steelmaking continuous casting and mold produced thereby |
| JP2971790B2 (en) * | 1995-10-16 | 1999-11-08 | 日本碍子株式会社 | Casting mold with excellent thermal conductivity-hardness balance |
| DE69606755T2 (en) * | 1995-11-17 | 2000-07-13 | Ngk Insulators Ltd | Mold made of a copper alloy for aluminum or its alloys |
| FR2750438B1 (en) * | 1996-06-27 | 1998-08-07 | Usinor Sacilor | METHOD AND INSTALLATION FOR ELECTROLYTIC COATING WITH A METAL LAYER OF THE SURFACE OF A CYLINDER FOR CONTINUOUS CASTING OF THIN METAL STRIPS |
| DE10018504A1 (en) * | 2000-04-14 | 2001-10-18 | Sms Demag Ag | Use of a hardenable copper alloy containing beryllium and nickel for molds for producing plates for thin slab continuous casting molds |
| DE10156925A1 (en) * | 2001-11-21 | 2003-05-28 | Km Europa Metal Ag | Hardenable copper alloy as a material for the production of casting molds |
-
2002
- 2002-10-25 TW TW091124995A patent/TW590822B/en not_active IP Right Cessation
- 2002-10-28 CA CA2410245A patent/CA2410245C/en not_active Expired - Lifetime
- 2002-11-05 MX MXPA02010879A patent/MXPA02010879A/en not_active Application Discontinuation
- 2002-11-14 EP EP02025371.2A patent/EP1314495B1/en not_active Expired - Lifetime
- 2002-11-14 US US10/294,357 patent/US20030094219A1/en not_active Abandoned
- 2002-11-19 CN CN02151419A patent/CN1419982A/en active Pending
- 2002-11-19 BR BR0204713-6A patent/BR0204713A/en not_active Application Discontinuation
- 2002-11-20 NO NO20025563A patent/NO340437B1/en not_active IP Right Cessation
- 2002-11-20 JP JP2002336609A patent/JP4295492B2/en not_active Expired - Lifetime
- 2002-11-20 KR KR1020020072434A patent/KR100961239B1/en active IP Right Grant
Also Published As
| Publication number | Publication date |
|---|---|
| EP1314495B1 (en) | 2017-01-11 |
| CA2410245C (en) | 2017-03-21 |
| KR100961239B1 (en) | 2010-06-03 |
| BR0204713A (en) | 2003-09-16 |
| CN1419982A (en) | 2003-05-28 |
| EP1314495A2 (en) | 2003-05-28 |
| JP4295492B2 (en) | 2009-07-15 |
| MXPA02010879A (en) | 2004-07-16 |
| NO340437B1 (en) | 2017-04-24 |
| TW590822B (en) | 2004-06-11 |
| US20030094219A1 (en) | 2003-05-22 |
| KR20030041833A (en) | 2003-05-27 |
| EP1314495A3 (en) | 2003-12-10 |
| NO20025563D0 (en) | 2002-11-20 |
| JP2003191056A (en) | 2003-07-08 |
| NO20025563L (en) | 2003-05-22 |
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