EP0069421A1 - Procédé de fabrication d'un demi-produit ou d'un produit fini à partir d'un matériau métallique par déformation à chaud - Google Patents

Procédé de fabrication d'un demi-produit ou d'un produit fini à partir d'un matériau métallique par déformation à chaud Download PDF

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Publication number
EP0069421A1
EP0069421A1 EP82200780A EP82200780A EP0069421A1 EP 0069421 A1 EP0069421 A1 EP 0069421A1 EP 82200780 A EP82200780 A EP 82200780A EP 82200780 A EP82200780 A EP 82200780A EP 0069421 A1 EP0069421 A1 EP 0069421A1
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EP
European Patent Office
Prior art keywords
temperature
workpiece
hot
shaping
deformed
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.)
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Application number
EP82200780A
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German (de)
English (en)
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EP0069421B1 (fr
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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Publication date
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Priority to AT82200780T priority Critical patent/ATE19531T1/de
Publication of EP0069421A1 publication Critical patent/EP0069421A1/fr
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Publication of EP0069421B1 publication Critical patent/EP0069421B1/fr
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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.
  • the invention is based on the object of specifying a hot molding process for metallic materials which, with great simplicity, allows the production of semifinished or finished parts in as few steps as possible and, thanks to good mold filling capacity, allows the design limits to be expanded.
  • the process is believed to work on a variety of plants substances can be used.
  • 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.
  • the horizontal at level 1 indicates the solidus temperature T sol of the material (alloy) to be deformed, which must not be reached under all circumstances during the entire working process. Otherwise local melting would occur and the connection and controlled structure of the workpiece would be lost.
  • 2 is the maximum temperature which - mostly at the end of the shaping - can be reached by the workpiece and the tool at the same time. Depending on the alloy and type of workpiece, it must always be below a certain amount. 1 (T sol ) stay.
  • 3 represents the homogenization temperature temperature of the workpiece r there, for which the same as applies to temperature 2, so that later certainly incipient melting are avoided during forming.
  • a radial compressor wheel with a diameter of 180 mm was produced in one operation by isothermal high-temperature pressing from a disc-shaped cylindrical blank.
  • the aluminum alloy used corresponded to US AA standard 2618 and had the following composition:
  • 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 preliminary 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 carried out as an isothermal high-temperature die press 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 0 ⁇ 10 0 C by being pushed into the associated induction coil.
  • the blank was then placed in the die heated to 480 ° - 520 ° C.
  • the pressing speed was set to an average value of approx. 0.5 - 1 mm / s.
  • 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.
  • the mean pressing pressure was approximately 120 MPa.
  • the solidus temperature is 549 ° C
  • the solution annealing temperature is 530 0 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.
  • Nimonic-80A had the following composition:
  • 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 hours and then quenched in water.
  • the hydraulic press provided for carrying out the operation was constructed similarly 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 I.
  • lock chambers which enabled the transition between the press room and the outside world.
  • the blank was first heated to a temperature of 1100 ° l and 20 ° C in the associated induction coil then placed in the TZM die heated to 1150 0 - 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 burr section (phase II). After reaching the maximum force, this value was reached for about 5 minutes until the mold was finally filled. kept constant (phase III). 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 0 - 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 turbine blade of 200 mm in length and 50 mm in width was produced in one operation by isothermal high-temperature pressing from a rod section.
  • the iron alloy used had the following composition:
  • Example II 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 II.
  • the workpiece temperature after preheating was approx. 1150 ° C, that of the TZM tools (die upper and lower part) 1150 0 - 1200 o C. All other parameters were observed in a similar way to Example II (deformation phases I-III).
  • the oxidic dispersoids Y 2 0 3 and TiO 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).
  • a round rod of 5 mm in diameter was produced by isothermal high-temperature extrusion from a press bolt of 20 mm in diameter.
  • the shape memory alloy used had the following composition:
  • 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. Then it was heated to a temperature of 850 ° C and at a temperature of 850 ° - 950 ° C by a matrix made of a nickel-based alloy (trade name IN-100) to 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.
  • T sol solidus temperature in degrees Kelvin
  • the temperature difference in the workpiece cross-section and over the entire time of the isothermal / quasi-isothermal shaping should be at most 500C and the rate of deformation 4 from 0 to 10s -1 , whereby 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.
  • the 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 shaping should advantageously be carried out in a temperature range in which, in addition to a first phase present as the main structural component, there is also 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 O 3 , TiO 2 , A1 2 0 3 etc., or of an ordinary oxide or of a carbide.
  • aluminum alloys, copper alloys (in particular Cu / Al / Ni), nickel-based superalloys, nickel-based dispersion alloys and nickel alloys of the Ni / Ti type (memory alloys) or Ni / Ti / Cu can be formed.
  • the method can also be applied to heat-resistant, rustproof ferritic, ferritic-austenitic and austenitic steels, in particular 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 Procédé de fabrication d'un demi-produit ou d'un produit fini à partir d'un matériau métallique par déformation à chaud Expired EP0069421B1 (fr)

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 true EP0069421A1 (fr) 1983-01-12
EP0069421B1 EP0069421B1 (fr) 1986-04-30

Family

ID=4272115

Family Applications (1)

Application Number Title Priority Date Filing Date
EP82200780A Expired EP0069421B1 (fr) 1981-06-26 1982-06-23 Procédé de fabrication d'un demi-produit ou d'un produit fini à partir d'un matériau métallique par déformation à chaud

Country Status (8)

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

Citations (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 (fr) * 1974-01-25 1975-08-22 Crucible Inc
US3975219A (en) * 1975-09-02 1976-08-17 United Technologies Corporation Thermomechanical treatment for nickel base superalloys
FR2298605A1 (fr) * 1975-01-24 1976-08-20 Mitsubishi Heavy Ind Ltd Procede pour le travail a la presse des metaux

Patent Citations (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 (fr) * 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
DE3270846D1 (en) 1986-06-05
KR840000655A (ko) 1984-02-25
KR890003976B1 (ko) 1989-10-14
PL237150A1 (en) 1983-02-14
EP0069421B1 (fr) 1986-04-30
JPS6360819B2 (fr) 1988-11-25
ATE19531T1 (de) 1986-05-15
BR8207730A (pt) 1983-05-31
WO1983000168A1 (fr) 1983-01-20
JPS58501041A (ja) 1983-06-30

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