EP0499117B1 - Verfahren zum kontinuierlichen Stranggiessen von Kupferlegierungen - Google Patents

Verfahren zum kontinuierlichen Stranggiessen von Kupferlegierungen Download PDF

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Publication number
EP0499117B1
EP0499117B1 EP92101770A EP92101770A EP0499117B1 EP 0499117 B1 EP0499117 B1 EP 0499117B1 EP 92101770 A EP92101770 A EP 92101770A EP 92101770 A EP92101770 A EP 92101770A EP 0499117 B1 EP0499117 B1 EP 0499117B1
Authority
EP
European Patent Office
Prior art keywords
casting
copper
process according
chill
tin
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
Application number
EP92101770A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP0499117A3 (en
EP0499117A2 (de
Inventor
Andreas Dr.-Ing. Krause
Horst Dipl.-Ing. Gravemann
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
KM Europa Metal AG
Original Assignee
KM Kabelmetal AG
KM Europa Metal AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by KM Kabelmetal AG, KM Europa Metal AG filed Critical KM Kabelmetal AG
Publication of EP0499117A2 publication Critical patent/EP0499117A2/de
Publication of EP0499117A3 publication Critical patent/EP0499117A3/de
Application granted granted Critical
Publication of EP0499117B1 publication Critical patent/EP0499117B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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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
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/004—Copper alloys
    • 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
    • B22D11/11—Treating the molten metal
    • B22D11/114—Treating the molten metal by using agitating or vibrating means
    • B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
    • 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
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/122—Accessories for subsequent treating or working cast stock in situ using magnetic fields

Definitions

  • the invention relates to a process for the continuous casting of thin slabs or round blocks with a diameter of 8 to 40 mm from copper alloys which tend to separate during solidification.
  • copper-nickel-tin alloys with higher nickel and tin contents tend to form strong segregations during solidification in a conventional casting process.
  • the cast structure is relatively coarse-grained, the grain diameter being in the cm range and the dendrite arms being relatively large apart at about 100 »m.
  • a casting structure with strong fluctuations in the composition, such as those caused by segregation, must be homogenized sufficiently before it can be further processed by forming.
  • the annealing time for the unfavorable casting structure of a copper-nickel-tin alloy with approximately 15% nickel and 8% tin for a homogenization treatment carried out at a temperature of approximately 900 ° C. is several weeks. It is generally known that the structure of a material due to grain growth increases with increasing duration and / or temperature of the annealing treatment coarsened. Grain coarsening, however, means that the deformability of a material deteriorates even further.
  • the invention has for its object to provide a casting process with which copper alloys with a strong tendency to segregate or are difficult to deform, for example higher alloyed copper-nickel-tin alloys, can be produced continuously and thus economically without the subsequent processing of Cast strands to ribbons, rods or wires encounter difficulties.
  • the increase in the electrical conductivity of the solidified metal compared to the liquid melt is significantly greater with the copper alloy than with steel. Because of the larger strand shell thickness and the significantly higher electrical conductivity compared to the melt, there is a much stronger shielding effect of the melt to be stirred by the strand shell for the electromagnetic fields of the stirring coils. Because of the relatively thick strand shell, a stirring device would have to be accommodated in the mold area. However, there is a further shielding effect due to the copper mold plates, which are usually 30 mm or thicker for reasons of stability.
  • Casting processes are also known in which the solidifying melt is stirred inductively. It is this so-called levitation process, in which the melt is held by magnetic fields during solidification without contacting the mold walls. Examples of this are the horizontal casting of flat ingots or the vertical upward casting of strands.
  • the mold used for the process according to the invention has very thin, coolable mold walls of only a few mm in thickness.
  • the outer mold wall preferably has a stiffening by means of a rib profile.
  • the mold wall and the rib profile were designed so that the electromagnetic fields of a stirring coil are shielded only relatively little.
  • the mold cavity of this mold was made with a thin graphite lining of about 3 mm, which provides only very little resistance to heat dissipation.
  • the graphite lining was rounded on the outside and was brought into intensive contact with the cooled mold wall by mechanical tensioning.
  • a 3-phase induction coil was arranged on the cooled outside of the mold, with which the melt inside the mold could be stirred inductively.
  • the direction of stirring could be chosen so that the melt on the sides of the mold was moved in the direction of withdrawal and could flow back in the center of the mold, and vice versa.
  • Melt was introduced into the mold cavity, which then, like in conventional continuous casting, had intensive contact with the mold walls.
  • the melt was stirred during the solidification and the solidified strand was removed at the other end of the mold.
  • the solidified strand moved alternately back and forth in relation to the mold surface, the forward stroke being greater than the reverse stroke.
  • a strand of 14 mm thickness was cast in a continuous casting process at 0.25 m / min with a consistently smooth surface. Due to the intensive contact with the mold wall and the small strand thickness, the cooling conditions were so good that the melt solidified relatively quickly even inside the strand without any significant oozing out or grain enlargement.
  • a small strand thickness is of great importance for the method according to the invention, since a copper alloy has only a low thermal conductivity in the range from 1 to 10% of the conductivity of copper. For this reason, heat removal from the inside of the strand is somewhat impeded. If the strand thickness is too great, there is also the risk that increased segregation and grain growth will occur inside the strand.
  • Adequate stirring action and good solidification of the melt can surprisingly be reconciled if the strand thickness is in the range from 8 mm to 40 mm.
  • the intensity of the inductive stirring of the melt is also of great importance. If the stirring intensity is too low, insufficient foreign germs are provided as nucleating agents by broken dendrite parts within the melt. The result of insufficient stirring intensity is a coarse-grained structure that is unfavorable for further processing. On the other hand, excessive stirring intensity also has considerable disadvantages, since this is associated with a high introduction of energy into the strand due to the induced eddy currents.
  • the stirring intensity can be described by the amount of energy that is introduced into the metal to be cast by the stirrer per unit of time. This amount of energy can be measured with the aid of a metallic test specimen which is introduced into the mold and has the same conductivity and spatial dimensions as the metal which is introduced into the mold during the casting process. If the stirring coil is excited, this leads to an increase in temperature in the test specimen. The power input can then be calculated from this temperature rise.
  • the stirring power introduced is in the range from 0.5 to 100 W / cm 3, preferably in the range from 5 to 70 W / cm 3.
  • the stirring power is based on a volume element of the metal to be cast, which is located - in the direction of withdrawal - between the front and rear limits of the stirring coil.
  • the average pull-off speed must not be too high, since then the bottom of the melt which has not yet solidified will become too long and narrow.
  • the consecutive solidification fronts then slow down the stirring speed of the viscous melt in the interior of the strand, so that the interior of the strand solidifies virtually without stirring.
  • the average pull-off speed must therefore be in the range from 0.05 to a maximum of 1.3 m / min, preferably in the range from 0.2 to 0.7 m / min.
  • the strand can be drawn off continuously, the mold oscillating with advantage.
  • the strand can also be withdrawn from the non-moving mold using the "push-pull" method.
  • the relative movement between the strand and the mold is essential.
  • the strand moves - relative to the mold - periodically a larger piece forward (forward stroke) and then a smaller piece back again (return stroke).
  • forward stroke forward stroke
  • return stroke return stroke
  • the strand shell is compressed during the return stroke, as a result of which it is also pressed against the mold walls, which improves the heat transfer.
  • a cast copper-nickel-tin strand can be produced which has an extremely fine-grained structure. Individual grains are no longer visible to the naked eye in a longitudinal section. Due to the favorable solidification conditions, the excretions are also very small and finely divided. The cast strand can therefore be processed without difficulty.
  • a thin slab made of a copper-nickel-tin alloy with 15% nickel and 8% tin was continuously cast using a very thin-walled continuous casting mold made of a hardenable copper-chromium-zirconium alloy, the mold cavity of which was lined with 3 mm thick graphite plates.
  • the slab was 14 mm thick and 80 mm wide.
  • the casting speed was about 0.25 m / min, while the stirring power averaged over the cross section of the mold cavity was set at 20 to 30 W / cm3.
  • the macrostructure is shown in a longitudinal section through the cast strand (FIG. 1). It can be seen that the cast strand has a uniform and extremely fine-grained structure over the entire cross-section, the maximum grain size being 0.05 mm.
  • FIG. 1 A further longitudinal section is shown in FIG. In comparison to FIG. 1, it shows the casting structure of a strand of a corresponding copper alloy, in which the melt was not stirred electromagnetically.
  • the grain size of this cast structure is several mm.
  • the strand cast by the process according to the invention could be cold-formed by 70 to 80% without cracking after milling the surface without homogenization. Hot forming was also carried out after brief homogenization at 800 to 850 ° C.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Continuous Casting (AREA)
  • Conductive Materials (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)
EP92101770A 1991-02-09 1992-02-04 Verfahren zum kontinuierlichen Stranggiessen von Kupferlegierungen Expired - Lifetime EP0499117B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE4103963A DE4103963A1 (de) 1991-02-09 1991-02-09 Verfahren zum kontinuierlichen stranggiessen von kupferlegierungen
DE4103963 1991-02-09

Publications (3)

Publication Number Publication Date
EP0499117A2 EP0499117A2 (de) 1992-08-19
EP0499117A3 EP0499117A3 (en) 1992-09-30
EP0499117B1 true EP0499117B1 (de) 1995-08-09

Family

ID=6424723

Family Applications (1)

Application Number Title Priority Date Filing Date
EP92101770A Expired - Lifetime EP0499117B1 (de) 1991-02-09 1992-02-04 Verfahren zum kontinuierlichen Stranggiessen von Kupferlegierungen

Country Status (8)

Country Link
US (1) US5265666A (ja)
EP (1) EP0499117B1 (ja)
JP (1) JP3073589B2 (ja)
AT (1) ATE126109T1 (ja)
CA (1) CA2060860C (ja)
DE (2) DE4103963A1 (ja)
ES (1) ES2076571T3 (ja)
FI (1) FI97109C (ja)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0988908A1 (de) * 1998-09-22 2000-03-29 KM Europa Metal AG Verfahren zur Lokalisierung von Elementkonzentrationen in einem Gussstrang und Anordnung zur Durchführung des Verfahrens

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102006027844B4 (de) * 2005-06-22 2019-10-31 Wieland-Werke Ag Kupferlegierung auf der Basis von Kupfer und Zinn
DE102012013817A1 (de) * 2012-07-12 2014-01-16 Wieland-Werke Ag Formteile aus korrosionsbeständigen Kupferlegierungen
ES2619840B1 (es) * 2017-03-31 2018-01-09 La Farga Lacambra, S.A.U. Agitador electromagnético para uso en sistemas de colada continua vertical, y uso del mismo
CN108453222B (zh) * 2018-03-12 2019-11-05 东北大学 一种铜基弹性合金薄带的减量化制备方法
CN110885938B (zh) * 2019-12-04 2021-06-01 中色奥博特铜铝业有限公司 一种5G通讯用Cu-Ni-Sn合金带箔材及其制备方法
CN116411202A (zh) * 2021-12-29 2023-07-11 无锡市蓝格林金属材料科技有限公司 一种铜锡合金线材及其制备方法

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH650429A5 (de) * 1980-10-30 1985-07-31 Concast Holding Ag Verfahren zum stranggiessen von stahl, insbesondere von brammen.
JPS57149052A (en) * 1981-03-09 1982-09-14 Sumitomo Light Metal Ind Ltd Method and device for continuous casting of metal
US4373970A (en) * 1981-11-13 1983-02-15 Pfizer Inc. Copper base spinodal alloy strip and process for its preparation
KR950014347B1 (ko) * 1986-02-27 1995-11-25 에스 엠 에스 슐레만-지이마크 악티엔게젤샤프트 강대주조공장에 있어서의 주조방법 및 장치
JPH01166868A (ja) * 1987-12-22 1989-06-30 Chuetsu Gokin Chuko Kk 連続鋳造装置
CH678026A5 (ja) * 1989-01-19 1991-07-31 Concast Standard Ag

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0988908A1 (de) * 1998-09-22 2000-03-29 KM Europa Metal AG Verfahren zur Lokalisierung von Elementkonzentrationen in einem Gussstrang und Anordnung zur Durchführung des Verfahrens

Also Published As

Publication number Publication date
EP0499117A3 (en) 1992-09-30
FI97109C (fi) 1996-10-25
EP0499117A2 (de) 1992-08-19
JPH07164109A (ja) 1995-06-27
US5265666A (en) 1993-11-30
FI920521A0 (fi) 1992-02-07
JP3073589B2 (ja) 2000-08-07
ES2076571T3 (es) 1995-11-01
CA2060860A1 (en) 1992-08-10
DE4103963A1 (de) 1992-08-13
ATE126109T1 (de) 1995-08-15
DE59203148D1 (de) 1995-09-14
FI920521A (fi) 1992-08-10
CA2060860C (en) 1998-06-23
FI97109B (fi) 1996-07-15

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