EP0035681A1 - Use of a steel having high strength and toughness - Google Patents

Use of a steel having high strength and toughness Download PDF

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EP0035681A1
EP0035681A1 EP81101268A EP81101268A EP0035681A1 EP 0035681 A1 EP0035681 A1 EP 0035681A1 EP 81101268 A EP81101268 A EP 81101268A EP 81101268 A EP81101268 A EP 81101268A EP 0035681 A1 EP0035681 A1 EP 0035681A1
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steel
cooling
forging
components
values
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German (de)
French (fr)
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EP0035681B1 (en
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Helmut Dr. Ing. Brandis
Dr. Ing. Serosh
Albert Dr. Ing. Von Den Steinen
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Thyssen Stahl AG
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Thyssen Edelstahlwerke AG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

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  • the invention relates to the use of a steel as a material for components which, after cooling in still or moving air, if necessary after controlled cooling from forging temperatures or annealing temperatures above 1150 0 C having a structure of ferrite and pearlite and thereby stretching inclin- 0, 2 -Limit values of at least 490 N / mm and a notched bar impact work (measured on the DVM sample) of at least 30 J.
  • the characteristic of this steel is that after forging it at temperatures between 1000 and 1250 ° C, preferably in a die between 1180 and 1250 ° C, with subsequent storage in still or moving air, a minimum 0, 2 limit of 450 N / mm 2 - achieved without subsequent heat treatment. This value is caused by the precipitation hardening of vanadium carbides or carbonitrides.
  • the impact strength of this material is low, so that its use is limited to certain components, such as the crankshaft and the connecting rod, for which mechanical properties other than toughness are paramount.
  • Typical characteristic values, which at 49 MnVS 3 after annealing at approx. 1225 ° C and after forging in the die to achieve crankshafts are listed in Example 1. After annealing at 1225 0 C, somewhat higher strength values are achieved with lower impact energy values than after forging in the die.
  • the strength values of the boundary can be varied by adjusting the analysis of carbon and manganese contents in the upper or lower region, while the impact energy values-especially after the annealing or forging at temperatures around 1200 0 C thereby are not significantly changed.
  • the object of this invention is therefore to provide a steel with improved toughness with similar strength values, this being achieved by simple air cooling of annealing or hot-forming temperatures without further heat treatment.
  • the steel is particularly suitable for objects with larger cross sections, the smallest cross section of which is at least 100 cm 2.
  • FIG. 4 Another example is the structure shown in Figure 4 of a steel containing silicon, manganese and vanadium, but with one Silicon content of 0.3%, which is below the range claimed in this patent.
  • grain sizes of 2 to 3 are also estimated according to ASTM and impact energy values between 10 and 14 J at a 0, 2 limit of approx. 500 N / mm 2 have been determined.
  • Ver facilitated steels g whose structure in the images 1 are displayed 3 and 4, lift clearly that low impact energy values (10-15 J) at 0, 2-limits 500-570 N / mm 2 can be achieved.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
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  • Organic Chemistry (AREA)
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Abstract

1. Use of a steel containing 0.3 to 0.4 % of carbon 0.65 to 1.2 % of silicon 0.55 to 1.3 % of manganese 0.05 to 0.18 % of vanadium 0 to 0.5 % of chromium 0 to 0.2 % of sulphur 0 to 0.1 % of aluminium 0 to 0.04 % of nitrogen, the remainder being iron, and impurities resulting from the melting process, as a material for components which, after cooling in still air, or in moving air, or, if appropriate, after controlled cooling from forging or annealing temperatures above 1,150 degrees C, possess a structure composed of ferrite or pearlite, associated with yield-point values and/or 0.2 % yield-strength values of not less than 490 N/mm2, and absorbed-energy values, measured in notched-bar impact tests on DVM-type test pieces, of not less than 30 J.

Description

Die Erfindung betrifft die Verwendung eines Stahls als Werkstoff für Bauteile, die nach dem Abkühlen an ruhender oder bewegter Luft gegebenenfalls nach gesteuerter Abkühlung von Schmiedetemperaturen oder von Glühtemperaturen über 11500C ein Gefüge aus Ferrit und Perlit aufweisen und dabei Streck- bzw- 0, 2-Grenzwerte von mindestens 490 N/mm und eine Kerbschlagarbeit (gemessen an der DVM-Probe) von mindestens 30 J haben.The invention relates to the use of a steel as a material for components which, after cooling in still or moving air, if necessary after controlled cooling from forging temperatures or annealing temperatures above 1150 0 C having a structure of ferrite and pearlite and thereby stretching bzw- 0, 2 -Limit values of at least 490 N / mm and a notched bar impact work (measured on the DVM sample) of at least 30 J.

Seit etwa 10 Jahren wird ein Stahl für geschmiedete Bauteile wie z. B. Kurbelwellen verwendet (DE-OS 23 50 370), der in Deutschland die Bezeichnung 49 MnVS 3 erhalten hat. Für ihn wird in der Stahl-Eisen-Liste (Werkstoff Nr. 1. 1199) nachstehender Analysenbereich angegeben:

Figure imgb0001
Steel has been used for forged components such as B. crankshafts used (DE-OS 23 50 370), which has received the designation 49 MnVS 3 in Germany. The following analysis range is specified for him in the steel-iron list (material no. 1199):
Figure imgb0001

Das Merkmal dieses Stahles ist, daß er nach dem Schmieden bei Temperaturen zwischen 1000 und 1250°C, vorzugsweise im Gesenk zwischen 1180 und 1250°C, mit anschließendem Ablegen an ruhender oder bewegter Luft eine Mindest-0, 2-Grenze von 450 N/mm2 - ohne eine nachträgliche Wärmebehandlung- erreicht. Dieser Wert wird durch die Ausscheidungshärtung von Vanadiumkarbiden oder -karbonitriden hervorgerufen.The characteristic of this steel is that after forging it at temperatures between 1000 and 1250 ° C, preferably in a die between 1180 and 1250 ° C, with subsequent storage in still or moving air, a minimum 0, 2 limit of 450 N / mm 2 - achieved without subsequent heat treatment. This value is caused by the precipitation hardening of vanadium carbides or carbonitrides.

Die Kerbschlagzähigkeit dieses Werkstoffes ist jedoch gering, so daß seine Verwendung sich auf bestimmte Bauteile, wie z.B. die Kurbelwelle und den Pleuel beschränkt, bei denen andere mechanische Eigenschaften als die Zähigkeit im Vordergrund stehen. Typische Kennwerte, die an 49 MnVS 3 nach dem Glühen bei rd. 1225°C und nach dem Schmieden im Gesenk zu Kurbelwellen erreicht werden, sind in Beispiel 1 aufgeführt. Nach dem Glühen bei 12250C werden etwas höhere Festigkeitswerte bei geringeren Kerbschlagarbeitswerten erzielt als nach dem Schmieden im Gesenk. Die Festigkeitswerte können durch Einstellen der Kohlenstoff- und Mangangehalte im oberen oder unteren Bereich der Grenzanalyse variiert werden, während die Kerbschlagarbeitswerte -insbesondere nach dem Glühen oder Schmieden bei Temperaturen um 12000C- dadurch nicht wesentlich verändert werden.However, the impact strength of this material is low, so that its use is limited to certain components, such as the crankshaft and the connecting rod, for which mechanical properties other than toughness are paramount. Typical characteristic values, which at 49 MnVS 3 after annealing at approx. 1225 ° C and after forging in the die to achieve crankshafts are listed in Example 1. After annealing at 1225 0 C, somewhat higher strength values are achieved with lower impact energy values than after forging in the die. The strength values of the boundary can be varied by adjusting the analysis of carbon and manganese contents in the upper or lower region, while the impact energy values-especially after the annealing or forging at temperatures around 1200 0 C thereby are not significantly changed.

Das Gefüge des 49 MnVS 3 nach der Behandlung 1225°C 0, 5 h/Luft (Beispiel 1) ist aus Bild 1 ersichtlich. Der voreutektoidische Ferrit liegt überwiegend auf den ehemaligen Austenitkorngrenzen, wodurch die Bestimmung der bei 12250C vorhandenen Korngröße ermöglicht wird. Nach der Bildrichtreihe von ASTM E 112 ist dieses Gefüge den Bildnummern 1 bis 3 zuzuordnen.The structure of the 49 MnVS 3 after the treatment at 1225 ° C 0.5 h / air (example 1) can be seen in Figure 1. The voreutektoidische ferrite is predominantly on the former austenite grain boundaries, thereby allowing the determination of the existing 1225 0 C grain size. According to the ASTM E 112 image alignment series, this structure can be assigned to image numbers 1 to 3.

Die Kerbschlagarbeit dieses Stahls ist jedoch für viele Verwendungszwecke zu niedrig.However, the impact energy of this steel is too low for many uses.

Dieser Erfindung liegt daher nun die Aufgabe zugrunde, einen Stahl mit verbesserter Zähigkeit bei ähnlichen Festigkeitswerten bereitzustellen, wobei dies durch einfache Luftabkühlung von Glüh- bzw. Warmformgebungstemperaturen ohne weitere Wärmebehandlung erreicht werden soll.The object of this invention is therefore to provide a steel with improved toughness with similar strength values, this being achieved by simple air cooling of annealing or hot-forming temperatures without further heat treatment.

Zur Lösung dieser Aufgabe wird die Verwendung eines Stahls der in den Ansprüchen angegebenen Analyse für den eingangs genannten Zweck vorgeschlagen. Besonders eignet sich der Stahl für Gegenstände mit größeren Querschnitten, deren kleinster Querschnitt mindestens 100 cm 2 beträgt.To solve this problem, the use of a steel of the analysis specified in the claims is proposed for the purpose mentioned at the beginning. The steel is particularly suitable for objects with larger cross sections, the smallest cross section of which is at least 100 cm 2.

Die Ergebnisse von Untersuchungen haben überraschenderweise gezeigt, daß durch eine bestimmte Kombination von Silizium, Mangan und Vanadium ein feinkörniges Gefüge nach dem Glühen von Temperaturen über 12000C mit anschließendem Ablegen an Luft erreicht werden kann. Dafür sind ein Siliziumgehalt von mindestens 0, 65 %, ein Vanadiumgehalt von wenigstens 0, 05 % und ein Mangangehalt von wenigstens 0, 55 % notwendig. Das durch diese Kombination der Legierungselemente erreichbare typische Gefüge nach dem Glühen bei 12250C ist in Bild 2 abgebildet, und die augenscheinlich wahrnehmbare- Korngröße liegt nach ASTM zwischen den Bildnummern 7 bis 8.The results of investigations have surprisingly shown that a fine combination of silicon, manganese and vanadium can be used to achieve a fine-grained structure after annealing at temperatures above 1200 ° C. with subsequent storage in air. This requires a silicon content of at least 0.65%, a vanadium content of at least 0.05% and a manganese content of at least 0.55%. The typical structure that can be achieved by this combination of the alloying elements after annealing at 1225 0 C is shown in Figure 2, and the apparently perceptible grain size lies between the numbers 7 to 8 according to ASTM.

Überraschend war auch die Feststellung, daß die allgemein angenommene Gleichwertigkeit von Niob und Vanadium im vorliegenden Fall nicht gilt. Vanadium wäre also durch Niob nicht ersetzbar. Die vorteilhaften Eigenschaften, die mit Vanadium erzielt werden, erreichen Stähle mit Niob statt Vanadium nicht.It was also surprising to find that the generally accepted equivalence of niobium and vanadium does not apply in the present case. Vanadium would therefore not be replaceable with niobium. Steels with niobium instead of vanadium do not achieve the advantageous properties that are achieved with vanadium.

Fehlt eines der Elemente Silizium, Mangan oder Vanadium, so wird die voreutektoidische Ferritbildung innerhalb der ehemaligen Austenitkörner unterdrückt, und es ergibt sich somit ein grobes Sekundärkorn.If one of the elements silicon, manganese or vanadium is missing, the pre-eutectoid ferrite formation within the former austenite grains is suppressed and a coarse secondary grain is thus obtained.

Dies veranschaulicht die Gefügeaufnahme in Bild 3, die von einem Stahl stammt mit den in diesem Patent beanspruchten Gehalten an Silizium und Mangan, jedoch ohne Vanadiumzusatz. Die Korngröße beträgt 2 bis 3 nach ASTM. In diesem Zustand ist eine 0, 2-Grenze von rd. 500 N/mm2 bei einer Kerbschlagarbeit von 10 bis 15 J, gemessen an der DVM-Probe, ermittelt worden.This is illustrated by the micrograph in Figure 3, which comes from a steel with the silicon and manganese contents claimed in this patent, but without the addition of vanadium. The grain size is 2 to 3 according to ASTM. In this state there is a 0, 2 limit of approx. 500 N / mm 2 with an impact energy of 10 to 15 J, measured on the DVM sample, were determined.

Ein weiteres Beispiel ist das in Bild 4 dargestellte Gefüge eines Silizium, Mangan und Vanadium enthaltenden Stahls, jedoch mit einem Siliziumgehalt von 0, 3 %, welcher unterhalb des in diesem Patent beanspruchten Bereichs liegt. In diesem Falle sind ebenfalls Korngrößen von 2 bis 3 nach ASTM geschätzt und Kerbschlagarbeitswerte zwischen 10 bis 14 J bei einer 0, 2-Grenze von rd. 500 N/mm2 bestimmt worden.Another example is the structure shown in Figure 4 of a steel containing silicon, manganese and vanadium, but with one Silicon content of 0.3%, which is below the range claimed in this patent. In this case, grain sizes of 2 to 3 are also estimated according to ASTM and impact energy values between 10 and 14 J at a 0, 2 limit of approx. 500 N / mm 2 have been determined.

Die Beispiele der Vergleichsstähle, deren Gefüge in den Bildern 1, 3 und 4 abgebildet sind, heben deutlich hervor, welche niedrigen Kerbschlagarbeitswerte (10-15 J) bei 0, 2-Grenzen zwischen 500 und 570 N/mm2 erzielt werden.The examples of the Ver facilitated steels g, whose structure in the images 1 are displayed 3 and 4, lift clearly that low impact energy values (10-15 J) at 0, 2-limits 500-570 N / mm 2 can be achieved.

Die günstige Wirkung des Gefüges des erfindungsgemäßen Stahls (Bild 2) auf die mechanischen Eigenschaften nach dem Glühen von 12250C mit anschließendem Ablegen an Luft wird anhand von zwei Beispielen verdeutlicht.The favorable effect of the structure of the steel according to the invention (Figure 2) on the mechanical properties after annealing at 1225 ° C. with subsequent storage in air is illustrated by two examples.

Beispiel 2Example 2

enthält die Kennwerte eines Stahls mit rd. 0, 35 % C und mit Silizium-und Mangangehalten im unteren beanspruchten Bereich. Bei 0, 2-Grenzen von rd. 500 N/mm -also ähnlich denjenigen der Vergleichsstähle mit den in Bildern 3 und 4 gezeigten Gefügen-, ergeben sich bedeutend höhere Kerbschlagarbeitswerte von rd. 38 J.contains the characteristic values of a steel with approx. 0, 35% C and with silicon and manganese contents in the lower stressed area. With 0, 2 limits of approx. 500 N / mm - similar to that of the comparative steels with the structure shown in Figures 3 and 4 - results in significantly higher notched bar impact values of approx. 38 yrs

Beispiel 3Example 3

Eine Erhöhung des Kohlenstoffgehaltes des erfindungsgemäßen Stahls von 0, 33 auf 0, 43 % führt zu einer höheren 0, 2-Grenze von rd. 570 N/mm2 bei Kerbschlagarbeitswerten von rd. 28 J. Verglichen mit 49 MnVS 3 (Beispiel 1) hat dieser Stahl eine fast dreifach höhere Kerbschlagarbeit bei praktisch gleicher 0, 2-Grenze.An increase in the carbon content of the steel according to the invention from 0.33 to 0.43% leads to a higher 0.2 limit of approx. 570 N / mm 2 with impact strength values of approx. 28 J. Compared to 49 MnVS 3 (example 1), this steel has an almost three times higher impact energy with practically the same 0, 2 limit.

Beispiel 4Example 4

Hier wurden Kennwerte, die an dem erfindungsgemäßen Stahl nach dem Walzen oder Schmieden in den üblichen Temperaturbereichen mit anschließendem Ablegen an Luft ermittelt. Dieser Stahl weist Silizium-und Mangangehalte an der oberen Grenze des beanspruchten Bereichs auf. Den aufgeführten Werten ist zu entnehmen, daß auch an größeren Querschnitten eine hohe 0, 2-Grenze, hier z. B, rd. 580 N/mm2. bei zugleich günstigen Kerbschlagarbeitswerten zu erzielen ist. Diese Werte liegen in der Größenordnung, die an niedriglegierten Baustählen erreicht werden, die aber einer aufwendigen Vergütungsbehandlung unterworfen werden müssen.Here, characteristic values were found on the steel according to the invention after rolling or forging in the usual temperature ranges then placed in air. This steel has silicon and manganese contents at the upper limit of the stressed range. The values listed show that even on larger cross-sections there is a high 0, 2 limit, here e.g. B, approx. 580 N / mm 2 . can be achieved with low impact energy values. These values are of the order of magnitude that can be achieved with low-alloy structural steels, which, however, have to be subjected to a complex treatment.

Beispiel 1example 1

Figure imgb0002
Figure imgb0002

Behandlungszustand

Figure imgb0003
Treatment status
Figure imgb0003

Beipiel 2Example 2

Figure imgb0004
Figure imgb0004

Beispiel 3Example 3

Figure imgb0005
Figure imgb0005

Beispiel 4Example 4

Figure imgb0006
Figure imgb0006

Claims (4)

1. Verwendung eines Stahls mit
Figure imgb0007
Rest Eisen und erschmelzungsbedingte Verunreinigungen als Werkstoff für Bauteile, die nach dem Abkühlen an ruhender oder bewegter Luft gegebenenfalls nach gesteuerter Abkühlung von Schmiedetemperaturen oder von Glühtemperaturen über 11500C ein Gefüge aus Ferrit oder Perlit aufweisen und dabei Streck- bzw. 0, 2-Grenzwerte von mindestens 490 N/mm2 und eine Kerbschlagarbeit (gemessen an der DVM-Probe) von mindestens 30 J haben.1. Using a steel with
Figure imgb0007
 Remainder iron and melting-related impurities as a material for components which, after cooling in still or moving air, possibly after controlled cooling of forging temperatures or annealing temperatures above 1150 0 C, have a structure made of ferrite or pearlite and thereby have stretching or 0, 2 limit values of at least 490 N / mm 2 and a notched bar impact work (measured on the DVM sample) of at least 30 J. 2. Verwendung eines Stahls mit
Figure imgb0008
Rest Eisen und erschmelzungsbedingte Verunreinigungen als Werkstoff für Bauteile, die nach dem Abkühlen an ruhender oder bewegter Luft oder nach gesteuerter Abkühlung von Schmiede- oder von Glühtemperaturen über 1150°C ein Gefüge aus Ferrit und Perlit besitzen und dabei Streck- bzw. 0, 2-Grenzwerte von mindestens 530 N/mm2 und eine Kerbschlagarbeit (gemessen an der DVM-Probe) von wenigstens 25 J aufweisen.2. Using a steel with
Figure imgb0008
 Remainder iron and melting-related impurities As a material for components that, after cooling in still or moving air or after controlled cooling of forging or annealing temperatures above 1150 ° C, have a structure made of ferrite and pearlite and thereby have stretching or 0, 2 limit values of at least 530 N. / mm 2 and a notched bar impact work (measured on the DVM sample) of at least 25 J. 3. Verwendung eines Stahls mit
Figure imgb0009
für Bauteile, die nach dem Warmumformen durch Walzen, Schmieden oder Pressen bei Endverformungstemperaturen unter 1150°C und anschließendem Abkühlen an ruhender oder bewegter Luft ein ferritischperlitisches Gefüge mit einer Streck- oder 0, 2-Grenze von mindestens 550 N/mm2 und einer Kerbschlag arbeit (gemessen an der DVM-Probe) von wenigstens 30 J aufweisen.3. Use a steel with
Figure imgb0009
 For components that work after hot forming by rolling, forging or pressing at final deformation temperatures below 1150 ° C and then cooling in still or moving air, a ferritic-pearlitic structure with a yield or 0, 2 limit of at least 550 N / mm2 and a notch impact (measured on the DVM sample) of at least 30 J. 4. Verwendung eines Stahls der Zusammensetzung, Behandlung und Eigenschaften nach Anspruch 3, als Werkstoff für Bauteile, deren kleinster Querschnitt mindestens 100 cm2 beträgt.4. Use of a steel of the composition, treatment and properties according to claim 3, as a material for components, the smallest cross section of which is at least 100 cm 2 .
EP81101268A 1980-03-12 1981-02-21 Use of a steel having high strength and toughness Expired EP0035681B1 (en)

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AT81101268T ATE3652T1 (en) 1980-03-12 1981-02-21 USING A STEEL OF HIGH STRENGTH AND Toughness.

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DE3009443 1980-03-12
DE3009443A DE3009443C2 (en) 1980-03-12 1980-03-12 Use of a steel of high strength and toughness

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0572246A1 (en) * 1992-05-29 1993-12-01 Imatra Steel Oy Ab Forging and a method for its manufacture
WO2008028447A1 (en) 2006-09-01 2008-03-13 Georgsmarienhütte Gmbh Steel, and processing method for the production of higher-strength fracture-splittable machine components
EP2764127B1 (en) 2011-10-07 2015-08-12 Babasaheb Neelkanth Kalyani A process to improve fatigue strength of micro alloy steels, forged parts made from the process and an apparatus to execute the process

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Publication number Priority date Publication date Assignee Title
DE3201204C2 (en) * 1982-01-16 1983-12-22 M.A.N. Maschinenfabrik Augsburg-Nürnberg AG, 8900 Augsburg "Use of a carbon-manganese steel for components with high strength and toughness with simple heat treatment"
DE102004022248B4 (en) * 2004-05-04 2007-06-14 Zf Friedrichshafen Ag Process for the production of balls or ball segments, as well as subsequently manufactured ball element for two-part ball studs

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US3173782A (en) * 1962-06-13 1965-03-16 Bethlehem Steel Corp Vanadium nitrogen steel
DE2210915A1 (en) * 1972-03-07 1973-09-20 Hoesch Werke Ag Evaporater tubes - by heat treating welded silicon manganese steel strip, for sugar mfr
DE2350370A1 (en) * 1973-10-08 1975-04-17 Volkswagenwerk Ag Forging carbon-manganese steel - micro-alloyed with vanadium or niobium and cooling in air at room temp.
GB1441695A (en) * 1974-03-04 1976-07-07 Towmotor Corp High strength steel

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GB1342582A (en) * 1970-03-20 1974-01-03 British Steel Corp Rail steel

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Publication number Priority date Publication date Assignee Title
US3173782A (en) * 1962-06-13 1965-03-16 Bethlehem Steel Corp Vanadium nitrogen steel
DE2210915A1 (en) * 1972-03-07 1973-09-20 Hoesch Werke Ag Evaporater tubes - by heat treating welded silicon manganese steel strip, for sugar mfr
DE2350370A1 (en) * 1973-10-08 1975-04-17 Volkswagenwerk Ag Forging carbon-manganese steel - micro-alloyed with vanadium or niobium and cooling in air at room temp.
GB1441695A (en) * 1974-03-04 1976-07-07 Towmotor Corp High strength steel

Non-Patent Citations (1)

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Title
TRANSACTIONS A.S.M.E., Serie B: Journal of engineering for industry, Band 93, Nr. 4, November 1971, Seiten 1169-1170 A.J. SCHILLER et al.: "The effects of vanadium in high srtength low alloy steels" *

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0572246A1 (en) * 1992-05-29 1993-12-01 Imatra Steel Oy Ab Forging and a method for its manufacture
WO2008028447A1 (en) 2006-09-01 2008-03-13 Georgsmarienhütte Gmbh Steel, and processing method for the production of higher-strength fracture-splittable machine components
JP2010501733A (en) * 2006-09-01 2010-01-21 ゲオルクスマリーエンヒュッテ ゲゼルシャフト ミット ベシュレンクテル ハフツング Steel for producing a mechanical member having higher strength and capable of breaking and separating, and processing method
AU2007294317B2 (en) * 2006-09-01 2011-10-13 Georgsmarienhutte Gmbh Steel, and processing method for the production of higher-strength fracture-splittable machine components
EP2764127B1 (en) 2011-10-07 2015-08-12 Babasaheb Neelkanth Kalyani A process to improve fatigue strength of micro alloy steels, forged parts made from the process and an apparatus to execute the process

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ATE3652T1 (en) 1983-06-15

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