EP0069421B1 - Verfahren zur Herstellung eines Halbzeugs oder eines Fertigteils aus einem metallischen Werkstoff durch Warm-Formgebung - Google Patents

Verfahren zur Herstellung eines Halbzeugs oder eines Fertigteils aus einem metallischen Werkstoff durch Warm-Formgebung Download PDF

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Publication number
EP0069421B1
EP0069421B1 EP82200780A EP82200780A EP0069421B1 EP 0069421 B1 EP0069421 B1 EP 0069421B1 EP 82200780 A EP82200780 A EP 82200780A EP 82200780 A EP82200780 A EP 82200780A EP 0069421 B1 EP0069421 B1 EP 0069421B1
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EP
European Patent Office
Prior art keywords
temperature
workpiece
hot
process according
alloy
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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
Application number
EP82200780A
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German (de)
English (en)
French (fr)
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EP0069421A1 (de
Inventor
Gernot Dr. Gessinger
Günther Dr. Schroeder
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.)
BBC Brown Boveri AG Switzerland
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BBC Brown Boveri AG Switzerland
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Priority to AT82200780T priority Critical patent/ATE19531T1/de
Publication of EP0069421A1 publication Critical patent/EP0069421A1/de
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    • 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

Definitions

  • the invention is based on a method for producing a semifinished product or a finished part according to the preamble of claim 1.
  • US-A-3 975 219 describes a method for the thermomechanical treatment of nickel superalloys.
  • a superplastic state in the range below the y 'solution annealing temperature is initially sought.
  • the hot pre-compacted blank is subjected to a gradual cooling down to room temperature via a salt bath and then reheated and an extrusion process just below the y'-solution annealing temperature.
  • Disks are cut from the extruded material and subjected to further hot forming by isothermal forging within a temperature range which is below, but at most 120 ° C lower than the ys' solution annealing temperature.
  • the deformation should be at least 10% (example 1: 83% decrease in height) and the rate of deformation should not exceed 0.017s- 1- (example 1: 0.0017s- 1 ).
  • the workpiece shaped in this way is then zone-annealed under a temperature gradient of approx. 1 ° C./mm and a temperature at the end of the workpiece which lies between the y'-solution annealing temperature and the solidus temperature in order to set a coarse grain structure.
  • This process which is specifically aimed at superalloys and the achievement of a coarse grain in the longitudinal direction of the workpiece, requires a superplastic condition beforehand and is characterized by numerous complex process steps.
  • the invention has for its object to provide a hot-forming process in general for metallic materials, wherein a workpiece initially made as a cast ingot, rolled ingot, forged blank or powder-metallurgically manufactured blank made of a metal alloy, except for a nickel-based superalloy which has been brought into the superplastic state, in as few steps as possible can be converted into a semi-finished or finished part. Thanks to the good mold filling capacity of the workpiece, the process should allow for great simplicity to expand the design limits and be applicable to a large number of materials.
  • the guiding principle of the invention is to deform the material as close as possible below the solidus temperature, but to avoid local liquefaction with the greatest care. This measure considerably reduces the yield stress (deformation resistance) of the material, so that optimum mold filling capacity is achieved.
  • the abscissa represents the time axis, the ordinate the temperature axis.
  • T sol solidus temperature of the material (alloy) to be deformed
  • 2 is the maximum temperature which - usually at the end of the shaping - can be reached by the workpiece and tool at the same time.
  • T sol the maximum temperature which - usually at the end of the shaping - can be reached by the workpiece and tool at the same time.
  • T sol represents the homogenization temperature of the workpiece, for which the same applies as for temperature 2, so that subsequent melting during the forming process can be avoided with certainty.
  • 4 is the course of the workpiece temperature over time until the end of the shaping. This operation breaks down into the preheating phase 8 and the forming phase 9.
  • 5 represents the course of the workpiece temperature with normal cooling to room temperature.
  • 6 is the analogous course after the shaping in the event that the latter is subjected to further additional heat treatment (eg heat aging, thermal hardening) etc.) is connected. In most cases, you will not be able to avoid homogenizing the material beforehand. However, this is not an absolutely necessary requirement for the method according to the invention, but it means a preferred safety measure.
  • the course of the temperature during the homogenization phase 10 is shown by the line 7.
  • a disc in the form of a rod section was used as the starting material.
  • the rod was made from a section of a larger diameter press stud made by extrusion by extrusion.
  • workpieces produced by open-die forging can also be used as preforms.
  • the shape of the compressor wheel to be produced had 18 radially standing blades, slightly curved on the circumference in the tangential direction, of approximately 30 mm depth, which had a wall thickness of approximately 4 mm at the base and one of approximately 2 mm at the head.
  • the disk-shaped wheel body had an axial wall thickness of approx. 6 mm on the circumference.
  • the raw material was subjected to a homogenization annealing at a temperature of 520 ° C. for 20 hours before the shaping. This measure serves to avoid local melting or local pore formation when the maximum temperature is subsequently passed during the deformation process. The latter was called isothermal. High-temperature die presses carried out on a specially designed hydraulic press equipped with inductive workpiece and tool heating.
  • the press was set up for low stamp speeds of 0.05 - 5 mm / s, which could be changed as required during the pressing. Furthermore, the pressing force could also be kept constant over a longer predetermined period of time after reaching a predetermined limit value.
  • the table and stamp were provided with a cooling device.
  • the inductive heating system consisted of an induction coil for heating the workpiece blank as well as the tools (dies) made of hot-work steel. Precise temperature control and temperature control was ensured via thermocouples in the tool and via buttons on the workpiece blank.
  • a specially designed device was used for transporting the workpiece into the heating zone or into the area of the tool, as well as for ejecting it from the tool after forming and transporting it to storage.
  • the workpiece blank in the form of a disk was first continuously heated to a temperature of 480 ° ⁇ 10 ° C by being pushed into the associated induction coil. The blank was then placed in the die heated to 480 ° - 520 ° C. Now the pressing speed was set to an average value of approx. 0.5 - 1 mm / s. During this first phase of upsetting, in which the workpiece temperature adapts to the tool temperature, the pressing force rose only slightly (from 0 to approx. 500 kN). The blades were then shaped in a second phase, the punch speed being reduced to 0.05-0.1 mm / s and the pressing force steadily increasing at the same time until it reached its maximum (approx. 3000 kN). The pressing force was now kept constant in order to completely fill the mold during this third phase, which lasted about 5 to 10 minutes. The pressing time for such a compressor wheel was approx. 10-20 min average pressing pressure was about 120 MPa.
  • the solidus temperature is 549 ° C
  • the solution annealing temperature is 530 ° C.
  • the undissolved intermetallic compound FeNiAl 9 still exists as an independent phase in this alloy. It prevents uncontrolled grain growth during high temperature shaping.
  • the deformation temperature of 480 ° - 520 ° C was optimally chosen in this regard and local pore formation due to melting was also not to be feared.
  • the shaping according to conventional forging technology which is carried out for the aforementioned aluminum alloy in the temperature range of approximately 410-450 ° C., is considerably less favorable.
  • the pressures here are between 200 and 500 MPa, which requires heavier and more powerful presses.
  • the mold filling capacity is significantly worse, so that the blades do not reach the target dimension (rib wall thickness 2 - 4 mm) by far and you have to make do with rib thicknesses of approx. 8 - 10 mm in the first work step. This requires at least a few additional work steps, including additional costly machining.
  • a section from a rolled bar was used as the starting material.
  • the primary material was first annealed under protective gas at a temperature of 1080 ° C. for 8 h and then quenched in water.
  • the hydraulic press intended to carry out the operation was constructed in principle in a similar manner to that described in Example I. It had an adjustment range for the stamp speed of 0.05 - 25 mm / s.
  • it was encapsulated in such a way that operation under protective gas or vacuum was possible.
  • dies made from the well-known molybdenum alloy TZM were used, which allow working temperatures up to over 1200 ° C.
  • the inductive heating was designed in the same way as that in example 1.
  • lock chambers which enabled the transition between the press room and the outside world.
  • the blank was first heated to an average temperature of 1100 ° C in the associated induction coil and then placed in the TZM die heated to 1150 ° - 1200 ° C.
  • the stamp was then pressed against the lower half of the die at a pressing speed of approx. 4 mm / s (phase I). After the pressing force began to increase, a further pressing was carried out at a pressing speed of approx. 0.1 mm / s to fill the ridge section (phase 11). After reaching the maximum force, this value was reached for about 5 minutes until the mold was finally filled. kept constant (phase 111). Depending on the shape and material, this phase can last approx. 1 - 10 min. The total pressing time for such a turbine blade can be approximately 2-15 minutes. In the present case, the mean pressing pressure reached the value of approx. 200 MPa.
  • the present nickel-based superalloy has a solidus temperature of approx. 1360 ° C and a solution annealing temperature of approx. 1080 ° C. In the temperature range of 1150 ° - 1200 ° C, which corresponds to a sufficiently large distance from the solidus line to prevent melting, there are still undissolved metal carbides in finely divided form. These prevent uncontrolled grain growth during high-temperature deformation, which could also be determined by comparing metallographic micrographs.
  • a section of an extruded rod was used as the starting material.
  • the alloy itself was produced in a known manner by powder metallurgy by mechanical alloying and subsequent compression by extrusion.
  • the blank was first homogenized at a temperature of 1150 ° C. for 15 minutes and cooled again to room temperature.
  • the further process steps were carried out in a manner analogous to that described in Example 11.
  • the workpiece temperature after preheating was approx. 1150 ° C, that of the TZM tools (upper and lower part of the die) was 1150 ° C-1200 ° C. All other parameters were adhered to in a manner similar to Example II (deformation phases I-III).
  • the oxidic dispersoids Y 2 0 3 and Ti0 2 which are present in submicroscopic form and distribution, are thermally stable up to over 1200 ° C and reliably prevent uncontrolled grain growth during the operations.
  • a finished part made in this way from a dispersion alloy is characterized by maximum density, ie absolute freedom from pores compared to the conventional type of workpiece directly produced by powder metallurgy (pressing + sintering, hot isostatic pressing).
  • the starting material used was a powder-metallurgically produced pre-compacted ingot produced by mechanical alloying from a Cu / Ni pre-alloy and aluminum with A1 2 0 3 , which served as a press bolt.
  • the press bolt was first homogenized at 950 ° C. for 1 h and cooled again to room temperature. Thereupon it was heated to a temperature of 850 ° C. and pressed at a temperature of 850 ° to 950 ° C. through a matrix made of a nickel-based alloy (trade name IN-100) to form a strand of 5 mm in diameter.
  • the presence of the A1 2 0 3 dispersoid in an ultrafine distribution prevents inadmissible grain growth during the pressing process.
  • the workpiece Before shaping, the workpiece is advantageously homogenized for 0.1 to 100 h at a temperature which corresponds to the highest effective deformation temperature, in order to avoid local melting and pore formation, and is cooled again to room temperature. Cooling after shaping can also be done by quenching to room temperature in water or oil. Furthermore, quenching, similar to thermal hardening, can also be carried out to a temperature above room temperature in a metal or salt bath with subsequent aging.
  • hot forming can be drop forging, hot pressing, hot extrusion or hot extrusion. The hot forming should advantageously be carried out in a temperature range in which, in addition to a first phase, which is the main structural component, there is a second phase which inhibits grain growth at least during the entire shaping time.
  • the latter can preferably consist, for example, of an oxidic dispersoid, such as Y 2 0 3 , Ti0 2 , A1 2 0 3 etc., or of an ordinary oxide or of a carbide.
  • an oxidic dispersoid such as Y 2 0 3 , Ti0 2 , A1 2 0 3 etc.
  • the process can also be applied to heat-resistant, rustproof ferritic, ferritic-austenitic and austenitic steels, especially use oxide dispersion hardened steels.
  • the raw material can also be in the raw state as a porous sintered body or as a green, cold-pressed body made of a sintered material, which is compressed, sintered and converted into the intended shape during the molding process

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  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Forging (AREA)
  • Moulds For Moulding Plastics Or The Like (AREA)
  • Adornments (AREA)
EP82200780A 1981-06-26 1982-06-23 Verfahren zur Herstellung eines Halbzeugs oder eines Fertigteils aus einem metallischen Werkstoff durch Warm-Formgebung Expired EP0069421B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT82200780T ATE19531T1 (de) 1981-06-26 1982-06-23 Verfahren zur herstellung eines halbzeugs oder eines fertigteils aus einem metallischen werkstoff durch warm-formgebung.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CH422481 1981-06-26
CH4224/81 1981-06-26

Publications (2)

Publication Number Publication Date
EP0069421A1 EP0069421A1 (de) 1983-01-12
EP0069421B1 true EP0069421B1 (de) 1986-04-30

Family

ID=4272115

Family Applications (1)

Application Number Title Priority Date Filing Date
EP82200780A Expired EP0069421B1 (de) 1981-06-26 1982-06-23 Verfahren zur Herstellung eines Halbzeugs oder eines Fertigteils aus einem metallischen Werkstoff durch Warm-Formgebung

Country Status (8)

Country Link
EP (1) EP0069421B1 (ko)
JP (1) JPS58501041A (ko)
KR (1) KR890003976B1 (ko)
AT (1) ATE19531T1 (ko)
BR (1) BR8207730A (ko)
DE (1) DE3270846D1 (ko)
PL (1) PL237150A1 (ko)
WO (1) WO1983000168A1 (ko)

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3519503A (en) * 1967-12-22 1970-07-07 United Aircraft Corp Fabrication method for the high temperature alloys
US3698962A (en) * 1971-04-30 1972-10-17 Crucible Inc Method for producing superalloy articles by hot isostatic pressing
FR2259159A1 (ko) * 1974-01-25 1975-08-22 Crucible Inc
FR2298605A1 (fr) * 1975-01-24 1976-08-20 Mitsubishi Heavy Ind Ltd Procede pour le travail a la presse des metaux
US3975219A (en) * 1975-09-02 1976-08-17 United Technologies Corporation Thermomechanical treatment for nickel base superalloys

Also Published As

Publication number Publication date
EP0069421A1 (de) 1983-01-12
KR890003976B1 (ko) 1989-10-14
JPS6360819B2 (ko) 1988-11-25
JPS58501041A (ja) 1983-06-30
ATE19531T1 (de) 1986-05-15
KR840000655A (ko) 1984-02-25
DE3270846D1 (en) 1986-06-05
PL237150A1 (en) 1983-02-14
BR8207730A (pt) 1983-05-31
WO1983000168A1 (en) 1983-01-20

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