CN1271228C - Copper alloy capable of ageing hardening - Google Patents
Copper alloy capable of ageing hardening Download PDFInfo
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- CN1271228C CN1271228C CNB031033067A CN03103306A CN1271228C CN 1271228 C CN1271228 C CN 1271228C CN B031033067 A CNB031033067 A CN B031033067A CN 03103306 A CN03103306 A CN 03103306A CN 1271228 C CN1271228 C CN 1271228C
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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
- B22D11/0637—Accessories therefor
- B22D11/0648—Casting surfaces
- B22D11/066—Side dams
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Continuous Casting (AREA)
- Chemically Coating (AREA)
- Dental Preparations (AREA)
- Molds, Cores, And Manufacturing Methods Thereof (AREA)
- Moulds For Moulding Plastics Or The Like (AREA)
- Conductive Materials (AREA)
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Abstract
An age-hardenable copper alloy made of 1.2 to 2.7 wt% cobalt, which is able to be partially replaced by nickel, 0.3 to 0.7 wt% beryllium, 0.01 to 0.5 wt% zirconium, optionally 0.005 to 0.1 wt% magnesium and/or iron and in some instances up to a maximum of 0.15% of at least one element from the group including niobium, tantalum, vanadium, hafnium, chromium, manganese, titanium and cerium. The remainder is copper and includes production-conditioned impurities and usual processing additives. This copper alloy is used as the material for producing mold blocks for the side dams of continuous strip-casting installations.
Description
The present invention relates to a kind of alloy age-hardenable of material of material piece (Bloecken) of the side dike that is used to prepare tape casting equipment (Bandgiessanlagen).
Worldwide target, particularly steel and coppersmith the industry target, casting as far as possible near the work in-process of final size to save heat and/or cold deformation step, caused the development of so-called Hazelett tape casting equipment before 1970, wherein metal melt solidifies in the slit of two bands that run parallel.The side dike is made of the mould material piece (Formbloecken) or the side dike material piece (Seitendammbloecken) of the metal that has T-slot in the known tape casting equipment in for example by US Patent specification 3 865 176, expect that wherein piece is arranged in the flexible band that for example is made of steel for no reason, longitudinally with water Cast Strip synchronous operation.At this, side dike material piece (dike material piece) defines by watering the die cavity that the Cast Strip forms.
In addition, be used for tape casting equipment by the known side dike chain that constitutes by the material piece that has groove and spring (Feder) among EP 0 974 413 A1.The advantage of this mould material piece that has groove and spring that further develops is the accurate alignment and the guiding of material piece in casting process, thereby improves the surface quality of watering the Cast Strip.For preventing to generate the too early wearing and tearing of incline to the material piece that cause by plastic deformation and crackle, a kind of suitable material must have high rigidity and intensity, fine grained texture and good anti-long-term softening intensity.Heat of solidification for the dispensing liquid metal melt produces also requires mould material block of material that high thermal conductivity is arranged.
What have decisive significance at last is, the fatigue property of material the best, and it will guarantee can not cause in the thermal stresses that the cooling again of leaving casting section back material piece produces the cracking of the material piece in the corner of the T-slot that is used to hold steel band and slots.Here extra high thermal stresses--is caused by disadvantageous geometrical shape and mass distribution--that-expectation can be present in the side dike material piece of the structure that has groove and spring.
If produced this crackle that causes by thermal shock (Thermoschock), after the very short time, corresponding mould material piece just falls down from the side dike chain of band casting machine, and the metal of fused solution flows out arbitrarily from die cavity like this, possible damage equipment part.For changing the mould material piece that damages, must stop whole belt casting equipment, casting cycle interrupts.
Be to detect the tendency that crackle produces, a kind of test method has been proved to be effectively, wherein mould material piece is carried out 500 ℃ of following thermal treatments of two hours, then at 20-25 ℃ quenching-in water.Even for repeated this thermal shock test, suitable material can not produce any crackle on the T-slot surface yet.
Introduced a kind of copper base alloy age-hardenable among EP 0 346 645 B1, it contains 1.6-2.4% nickel, 0.5-0.8% silicon, and the 0.01-0.2% zirconium, optionally maximum 0.4% chromium and/or maximum 0.2% iron, all the other are copper, comprise the impurity that preparation causes.If this known copper alloy is as the material of the master die material piece of the side dike of preparation tape casting equipment, it satisfies the precondition of high life in principle.For this Albatra metal-, provided following performance combination:
20 ℃ Rm:635-660MPa
500 ℃ Rm:286-372MPa
Brinell hardness: 185-191HB (being equivalent to about 195-210HV)
Specific conductivity: 41.4-43.4%IACS
In thermal shock test, do not crack.Advantage with respect to the copper base alloy that contains beryllium is possible manual drying finish grind mould material piece, because do not contain beryllium in lapping rejects.The post-treatment of the used side dike material piece that has groove and spring is wanted much expensive, and general requirement prevents to give off lapping rejects thus with machine (wetting) rinse bath and casting face (for example in closed cavities).Under such condition, may use the alloy that contains beryllium in principle.
But the shortcoming of the side dike piece material of the CuNiSiZr alloy formation of mentioning among EP 0 346 645 B1 is that under the very high machinery and thermal stresses in the pouring operation of tape casting equipment, incline and casting face are are easily worn and torn too early.This wearing and tearing--show as test-results---owing to the material softening of casting rib and face to the numerical value that is lower than 160HV.And the thermal shock resistance of known CuNiSiZr alloy when being used as the side dike material piece of trough of belt and spring always is not enough to effectively prevent the generation of crackle in the T-slot in casting is used.
From prior art, task of the present invention is based on, a kind of side dike material piece that is used to prepare tape casting equipment is provided, the alloy age-hardenable of the material of the side dike material piece of groove and spring structure particularly, itself in addition under high casting rate the thermal stress for conversion also be insensitive, and have high abrasion resistance properties or softening resistance energy and the generation of crackle in the T-slot had very high resistibility.
This task is achieved by such copper alloy, be that it contains the 1.2-2.7wt% cobalt, the 0.3-0.7wt% beryllium, the 0.01-0.5wt% zirconium, nonessential 0.005-0.2wt% magnesium and/or 0.005-0.2wt% iron and nonessential maximum 0.15% at least a element that is selected from niobium, tantalum, vanadium, hafnium, chromium, manganese, titanium and cerium, all the other are copper, comprise impurity and processing additives commonly used that preparation causes.
The invention still further relates to a kind of method that is used for preparing the side dike material piece of continuous band casting equipment from copper alloy capable of ageing hardening, wherein said copper alloy is made of following material: the 1.2-2.7wt% cobalt, the 0.3-0.7wt% beryllium, the zirconium of 0.01-0.5wt%, at least a niobium that is selected from of nonessential 0.005-0.2wt% magnesium and/or 0.005-0.2wt% iron and nonessential maximum 0.15wt%, tantalum, vanadium, hafnium, chromium, manganese, the element of titanium and cerium, all the other are copper, comprise impurity and processing additives commonly used that preparation causes, described method is characterised in that, blank cold deformation 5-40% after thermal distortion of casting, solution annealing under a certain temperature in 850-970 ℃ of scope then,, handled 0.5-16 hour 400-550 ℃ of following age hardening subsequently with the granularity recrystallization of maximum 0.5mm owing to the cold deformation process the preceding that is close to solution annealing according to ASTM E 112.
By using by the 1.2-2.7wt% cobalt, the 0.3-0.7wt% beryllium, the 0.01-0.5wt% zirconium, the copper of 0.005-0.2wt% magnesium and/or iron and surplus optionally, also comprise the copper base alloy that impurity that preparation causes and the processing additives of using always constitute, can guarantee that material has enough agehardenabilities to reach high strength, hardness and specific conductivity on the one hand.On the other hand, only require relatively little, the highest 40% cold deformation, the fine grained texture that has enough plasticity with adjusting.By the zirconium content of sublevel targetedly, both can improve fatigue performance, also can improve resistance toheat.
Further improve the mechanical property of side dike material piece, particularly improve tensile strength, can be advantageously by containing the 1.8-2.4wt% cobalt, the 0.45-0.65wt% beryllium, the 0.15-0.3wt% zirconium, the copper alloy of the highest 0.05wt% magnesium and/or the highest 0.1% iron is realized.
The present invention allows, and the cobalt of the highest 80% content can be substituted by nickel in the copper alloy.
If copper alloy contains at least a niobium that is selected from of maximum 0.15wt%, tantalum, vanadium, hafnium, chromium, manganese, the element of titanium and cerium can further improve the mechanical property of side dike material piece.Can add the reductor commonly used of maximum 0.03wt% equally, boron for example, lithium, calcium, aluminium and phosphorus can not have negative impact to the mechanical property of copper alloy of the present invention.
According to further embodiment, a part of zirconium content can be by at least a cerium that is selected from of maximum 0.15wt%, hafnium, niobium, tantalum, vanadium, chromium, the element substitution of manganese and titanium.
Advantageously, the material piece of the side dike that is used for the double belt casting equipment that constitutes by copper alloy of the present invention, pass through processing step: casting, thermal distortion, cold deformation at the most 40%, solution annealing and handle 400-550 ℃ of following age hardening prepared in 0.5-16 hour under a certain temperature in 850-970 ℃ of scope.
Particularly advantageously be, this Albatra metal-can be after thermal distortion cold deformation 5-30%.Here particularly preferably in the cold deformation degree of the 10-15% in the above-mentioned scope.
If the side dike material piece under age hardening state has 650MPa at least, the tensile strength of 700-900MPa particularly, at least 210HV, the particularly Vickers' hardness of 230-280HV, the specific conductivity of 40%IACS, particularly 45-60%IACS at least, 400MPa at least under 500 ℃, the high-temperature tensile strength of 450MPa at least particularly, lowest hardness is 160HV after shelving 500 hours under 500 ℃, is 0.5mm according to the maximum particle size of ASTM E 112.
Particularly preferably be, pressing the granularity of ASTM E 112 calculating between 30-90 μ m under the age hardening state by the side dike material piece of copper alloy of the present invention.
In addition, by will the casting blank after thermal distortion, cold deformation at the most 40%, solution annealing and handle the order of 0.5-16 hour such processing step 400-550 ℃ of following age hardening under a certain temperature in 850-970 ℃ of scope has successfully been eliminated observed very poor recrystallization behavior in thermal distortion and solution annealing are handled in known CuCoBe alloy in simple especially mode.Very poor recrystallization behavior in thermal distortion, causes for the unacceptable granularity of application target until the open grain structure structure that is higher than 1mm under solution annealing and the age hardening state when preparing the mould material piece that is made of the CuCoBe alloy.But if material carries out cold deformation to maximum 40% between thermal distortion and solution annealing are handled, preferably to maximum 15%, then this additional processing step causes the obviously weave construction of thinner crystalline substance.Corresponding series of trials is verified, the mould material piece that is used for the side dike of band casting machine, the material of cold deformation and solution annealing subsequently has the obvious thinner weave construction of granularity less than 0.5mm under recrystallization temperature, and be higher than about 40% higher cold deformation degree in solution annealing subsequently because secondary recrystallization causes grain coarsening, granularity is higher than 1mm.
According to embodiment the present invention is further set forth below.By alloy of the present invention (A, B and C) and three comparing embodiments (D, E and F) advantage by copper alloy of the present invention has been described with three.Following table 1 has provided the composition of the copper alloy of weight percent statement:
Table 1
| Alloy | Co(％) | Ni(％) | Be(％) | Zr(％) | Si(％) | Cr(％) | Cu(％) |
| A | 2.1 | - | 0.54 | 0.18 | - | - | Surplus |
| B | 2.2 | - | 0.56 | 0.24 | - | - | Surplus |
| C | 1.3 | 1.0 | 0.48 | 0.15 | - | - | Surplus |
| D | - | 2.0 | - | 0.16 | 0.62 | 0.34 | Surplus |
| E | 2.1 | - | 0.55 | - | - | - | Surplus |
| F | 1.0 | 1.1 | 0.62 | - | - | - | Surplus |
The composition of alloy D is meant known CuNiSi base alloy, and E and F are standardized CuCo2Be or CuCoNiBe material.
All copper alloys melt in induction crucible furnace, and being cast into diameter in continuous casting process is the circle material piece of 280mm.The embodiment alloy A, the circle material piece of B and C is in extrusion machine, be higher than under 900 ℃ the temperature, be squeezed into the flat rod that is of a size of 79 * 59mm, be stretched as the size of 75 * 55mm then with cross section minimizing 12%, the material piece of Comparative Examples alloy D, E and F directly is squeezed into the size of 75 * 55mm and no longer carries out extra cold deformation under uniform temp.Then, CuCoBe or CuCoNiBe material be 900-950 ℃ of following solution annealing, and in the temperature range between 450-550 ℃ age hardening 0.5-16 hour.
CuNiSi base alloy is 800-850 ℃ of following solution annealing, and age hardening under same condition.Under age hardening state, measure tensile strength Rm, vickers hardness hv 10, specific conductivity (alternate parameter of thermal conductivity), according to the size of particles of ASTM E 112, at thermotolerance Rm under 500 ℃ and the softening resistance that passes through Vickers' hardness (HV10) measurement after shelving 500 hours under 500 ℃.
Last test is of a size of the mould material piece (1) of 70 * 50 * 40mm and is of a size of the thermal shock behavior of the mould material piece (2) that has groove and spring of 70 * 50 * 47mm.For this reason, mould material piece is at first 500 ℃ of down annealing 2 hours, then at 20-25 ℃ quenching-in water.Then, the T-slot of material piece is checked the increase situation of crackle with bore hole and 10 power microscopes.
All test-results in following table 2, have been summed up.
Table 2:
| Alloy | Rm MPa | HV 10 | Specific conductivity % IACS | Granularity μ m | Rm (500℃) Mpa | At 500 ℃ of hardness HV10 after shelving 500 hours | Performance after the thermal shock test | |
| Material piece (1) material piece (2) | ||||||||
| A | 801 | 254 | 50 | 30-90 | 523 | 173 | Flawless | Flawless |
| B | 804 | 245 | 51.5 | 45-90 | 464 | 175 | Flawless | Flawless |
| C | 812 | 255 | 49.5 | 45-90 | 485 | 167 | Flawless | Flawless |
| D | 652 | 205 | 43 | 45-90 | 387 | 118 | Flawless | Crackle is arranged |
| E | 786 | 260 | 50.5 | The highest by 5000 | 423 | 150 | Crackle is arranged | Crackle is arranged |
| F | 807 | 248 | 48.5 | The highest by 3000 | 434 | 152 | Crackle is arranged | Crackle is arranged |
The extension of the crackle in the determined T-slot is 2-5mm for the mould material piece that classifies as crackle, and crack length is 10mm to the maximum under individual cases.By contrast as can be seen, compare with F with material E, press the copper alloy A that the present invention prepares with additional little cold deformation, B and C have the weave construction of wonderful especially all even thin crystalline substances when having the optimization performance, have the necessary resistibility to the crackle generation when being used as the mould material piece that has groove and spring.When using as common mould material piece, copper alloy of the present invention also has with respect to the softening resistance energy of the obvious improvement of known CuNiSi alloy D with respect to alloy E and F and has the softening resistance energy that improves some.
Therefore, be suitable for very highlightedly in casting cycle, standing the typically material of the mould material piece of the side dikes that are used for tape casting equipment of the thermal stresses of variation by copper alloy of the present invention as preparing all.This not only has the mould material piece of present use, also has the mould material piece according to the structure of the trough of belt of EP 0 974 413 A1 and spring.
Claims (8)
1. be used for preparing the method for the side dike material piece of continuous band casting equipment from copper alloy capable of ageing hardening, wherein said copper alloy is made of following material: the 1.2-2.7wt% cobalt, the 0.3-0.7wt% beryllium, the zirconium of 0.01-0.5wt%, at least a niobium that is selected from of nonessential 0.005-0.2wt% magnesium and/or 0.005-0.2wt% iron and nonessential maximum 0.15wt%, tantalum, vanadium, hafnium, chromium, manganese, the element of titanium and cerium, all the other are copper, comprise impurity and processing additives commonly used that preparation causes, described method is characterised in that, blank cold deformation 5-40% after thermal distortion of casting, solution annealing under a certain temperature in 850-970 ℃ of scope then,, handled 0.5-16 hour 400-550 ℃ of following age hardening subsequently with the granularity recrystallization of maximum 0.5mm owing to the cold deformation process the preceding that is close to solution annealing according to ASTM E 112.2. the process of claim 1 wherein that described copper alloy contains the 1.8-2.4wt% cobalt, the 0.45-0.65wt% beryllium, the 0.15-0.3wt% zirconium, the highest 0.05wt% magnesium, the highest 0.1wt% iron, all the other are copper, comprise impurity and processing additives commonly used that preparation causes.
3. claim 1 or 2 method, the cobalt of the highest 80% content of wherein said copper alloy is substituted by nickel.
4. claim 1 or 2 method, a part of zirconium content of wherein said copper alloy is by at least a cerium that is selected from of maximum 0.15wt%, hafnium, niobium, tantalum, chromium, manganese, the element substitution of titanium and vanadium.
5. claim 1 or 2 method, wherein said copper alloy is cold deformation 5-30% behind the processing step of thermal distortion.
6. the method for claim 5, wherein said copper alloy is cold deformation 10-15% behind the processing step of thermal distortion.
7. claim 1 or 2 method, wherein said copper alloy has the tensile strength of 650MPa at least under the age hardening state, at least the Vickers' hardness of 210HV, at least the specific conductivity of 40%IACS, the high-temperature tensile strength of 400MPa at least under 500 ℃, lowest hardness is 160HV after shelving 500 hours under 500 ℃.
8. the method for claim 7, wherein said copper alloy has the tensile strength of 700-900MPa under age hardening state, the Vickers' hardness of 230-280HV, the specific conductivity of 45-60%IACS, the high-temperature tensile strength of 450MPa at least under 500 ℃, lowest hardness is 160HV after shelving 500 hours under 500 ℃.
9. the method for claim 8, wherein said copper alloy are pressed granularity that ASTM E 112 calculates between 30-90 μ m.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE10206597A DE10206597A1 (en) | 2002-02-15 | 2002-02-15 | Hardenable copper alloy used as a material for blocks for the sides of strip casting mills contains alloying additions of cobalt, beryllium, zirconium, and magnesium and/or iron |
| DE10206597.7 | 2002-02-15 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1442500A CN1442500A (en) | 2003-09-17 |
| CN1271228C true CN1271228C (en) | 2006-08-23 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB031033067A Expired - Fee Related CN1271228C (en) | 2002-02-15 | 2003-01-22 | Copper alloy capable of ageing hardening |
Country Status (15)
| Country | Link |
|---|---|
| US (2) | US20030159763A1 (en) |
| EP (1) | EP1340564B1 (en) |
| JP (1) | JP4472933B2 (en) |
| KR (1) | KR100967864B1 (en) |
| CN (1) | CN1271228C (en) |
| AT (1) | ATE367229T1 (en) |
| BR (1) | BR0300445B1 (en) |
| CA (1) | CA2417546C (en) |
| DE (2) | DE10206597A1 (en) |
| DK (1) | DK1340564T3 (en) |
| ES (1) | ES2288572T3 (en) |
| MX (1) | MXPA03000218A (en) |
| PL (1) | PL198565B1 (en) |
| PT (1) | PT1340564E (en) |
| RU (1) | RU2301844C2 (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20060086437A1 (en) * | 2004-10-22 | 2006-04-27 | Russell Nippert | Method for manufacturing copper alloys |
| JP2008151270A (en) * | 2006-12-18 | 2008-07-03 | Kitz Sct:Kk | Metal diaphragm valve |
| 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 |
| CN101643867B (en) * | 2009-08-28 | 2011-11-23 | 镇江汇通金属成型有限公司 | High performance copper casting alloy and preparation method thereof |
| JP2011081764A (en) * | 2009-09-14 | 2011-04-21 | Panasonic Corp | Content receiver, content reproducer, content reproducing system, content writing method, expiration date determining method, program, and recording medium |
| DE102014224236A1 (en) | 2014-11-27 | 2016-06-02 | Sms Group Gmbh | Device for strip casting of metallic products |
| DE102016006824A1 (en) * | 2016-06-03 | 2017-12-07 | Wieland-Werke Ag | Copper alloy and its uses |
| RU2625193C1 (en) * | 2016-10-10 | 2017-07-12 | Юлия Алексеевна Щепочкина | Copper-based alloy |
| KR101810925B1 (en) | 2017-10-18 | 2017-12-20 | 주식회사 풍산 | Copper alloy strips having high heat resistance and thermal dissipation properties |
| CN112210692B (en) * | 2020-09-10 | 2021-12-17 | 新余市长城铜产品开发有限公司 | Beryllium bronze long guide rail and manufacturing method thereof |
| CN115233032B (en) * | 2022-08-01 | 2023-06-27 | 河南云锦空天特导新材料有限公司 | Copper alloy wire and preparation method and application thereof |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3865176A (en) * | 1973-09-28 | 1975-02-11 | Hazelett Strip Casting Corp | Casting method for twin-belt continuous metal casting machines |
| 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 |
| JPS6260879A (en) * | 1985-09-10 | 1987-03-17 | Ngk Insulators Ltd | Wear resistant copper alloy member |
| US4749548A (en) * | 1985-09-13 | 1988-06-07 | Mitsubishi Kinzoku Kabushiki Kaisha | Copper alloy lead material for use in semiconductor device |
| DE3773470D1 (en) * | 1986-11-13 | 1991-11-07 | Ngk Insulators Ltd | PRODUCTION OF COPPER-BERYLLIUM ALLOYS. |
| 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 |
| US6059905A (en) * | 1993-08-26 | 2000-05-09 | Ngk Metals Corporation | Process for treating a copper-beryllium alloy |
| EP0854200A1 (en) * | 1996-10-28 | 1998-07-22 | BRUSH WELLMAN Inc. | Copper-beryllium alloy |
| 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
- 2002-02-15 DE DE10206597A patent/DE10206597A1/en not_active Withdrawn
-
2003
- 2003-01-08 MX MXPA03000218A patent/MXPA03000218A/en active IP Right Grant
- 2003-01-18 DK DK03001084T patent/DK1340564T3/en active
- 2003-01-18 DE DE50307676T patent/DE50307676D1/en not_active Expired - Lifetime
- 2003-01-18 EP EP03001084A patent/EP1340564B1/en not_active Expired - Lifetime
- 2003-01-18 ES ES03001084T patent/ES2288572T3/en not_active Expired - Lifetime
- 2003-01-18 PT PT03001084T patent/PT1340564E/en unknown
- 2003-01-18 AT AT03001084T patent/ATE367229T1/en active
- 2003-01-22 CN CNB031033067A patent/CN1271228C/en not_active Expired - Fee Related
- 2003-01-28 CA CA2417546A patent/CA2417546C/en not_active Expired - Fee Related
- 2003-02-10 US US10/361,660 patent/US20030159763A1/en not_active Abandoned
- 2003-02-11 PL PL358681A patent/PL198565B1/en unknown
- 2003-02-12 JP JP2003033937A patent/JP4472933B2/en not_active Expired - Fee Related
- 2003-02-13 BR BRPI0300445-7A patent/BR0300445B1/en not_active IP Right Cessation
- 2003-02-13 KR KR1020030008977A patent/KR100967864B1/en not_active IP Right Cessation
- 2003-02-14 RU RU2003104534/02A patent/RU2301844C2/en not_active IP Right Cessation
-
2008
- 2008-06-02 US US12/156,604 patent/US20080240974A1/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| US20030159763A1 (en) | 2003-08-28 |
| BR0300445A (en) | 2004-08-17 |
| JP2004002967A (en) | 2004-01-08 |
| EP1340564A3 (en) | 2005-04-27 |
| CA2417546C (en) | 2015-03-31 |
| KR20030069066A (en) | 2003-08-25 |
| EP1340564B1 (en) | 2007-07-18 |
| CN1442500A (en) | 2003-09-17 |
| DE10206597A1 (en) | 2003-08-28 |
| PL358681A1 (en) | 2003-08-25 |
| ES2288572T3 (en) | 2008-01-16 |
| DE50307676D1 (en) | 2007-08-30 |
| BR0300445B1 (en) | 2011-07-26 |
| CA2417546A1 (en) | 2003-08-15 |
| PL198565B1 (en) | 2008-06-30 |
| MXPA03000218A (en) | 2004-10-29 |
| ATE367229T1 (en) | 2007-08-15 |
| KR100967864B1 (en) | 2010-07-05 |
| RU2301844C2 (en) | 2007-06-27 |
| JP4472933B2 (en) | 2010-06-02 |
| US20080240974A1 (en) | 2008-10-02 |
| PT1340564E (en) | 2007-09-03 |
| DK1340564T3 (en) | 2007-11-19 |
| EP1340564A2 (en) | 2003-09-03 |
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