EP1961832B1 - Use of a steel alloy as a substance for producing dynamically loaded tube components and tube component - Google Patents
Use of a steel alloy as a substance for producing dynamically loaded tube components and tube component Download PDFInfo
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- EP1961832B1 EP1961832B1 EP08002285A EP08002285A EP1961832B1 EP 1961832 B1 EP1961832 B1 EP 1961832B1 EP 08002285 A EP08002285 A EP 08002285A EP 08002285 A EP08002285 A EP 08002285A EP 1961832 B1 EP1961832 B1 EP 1961832B1
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- tube component
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- tube
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Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
- C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Definitions
- the invention relates to the use of a steel alloy as a material for the production of dynamically loaded pipe components and such a pipe component.
- stabilizers which are used to reduce the tendency of the body to curve and to influence the self-steering behavior. They stiffen the suspension in one-sided load, since the resistance of the material of the stabilizer of the side slope resiliently counteracts.
- Another example would be a torsionally loaded shaft.
- Stabilizers are to be assigned with regard to the type of stress straight torsion springs or torsion bars, since a stabilizer is twisted at different compression of the wheels about its longitudinal axis. From the EP 0 753 595 B1 it is known to produce stabilizers from pipes. This is what you do it a tube more favorable ratio of the moment of resistance against torsion to the tube mass compared to a solid rod advantage. In the optimum for the torsion ratio of wall thickness to diameter of the pipes, the materials used would have to maintain a higher by approximately a factor of 1.4 yield strength and tensile strength as materials of solid rods while maintaining the design in the vehicles structurally predetermined or usable outer diameter.
- Another essential factor for achieving a high permanent fatigue strength is the surface quality of the outer and inner surface of the tubes used.
- the best surface qualities have longitudinally welded and possibly subsequently cold drawn tubes made of rolled steel strip. In this case, the errors occurring in seamless drawn pipes, such as pleats, etc., avoided.
- this tensile strength is insufficient to compete with stabilizers of a higher strength solid material.
- Even the steel 34MnB5 steel used to date for tubes for the manufacture of stabilizers only achieves tensile strengths of up to 1,800 MPa, but with a relatively low fatigue strength.
- the state of the art also includes the EP 1 698 712 , which discloses a steel material for highly loaded springs, having the following composition: C 0.35 - 0.65%, Si 1.4 - 2.5%, Mn 0.1 - 1.0%, Cr> 2.0% , Ni> 1.0%, Cu> 1.0%, P> 0.020%, S> 0.020%, N> 0.006%, Al> 0.1% and balance iron. Although this steel also achieves strengths up to about 2,100 MPa. High Ti and Al contents involve the risk of reduced fatigue strength, which can be attributed to the formation of hard phases.
- Titanium contents in the range greater than 0.01% lead to the primary precipitation of hard titanium nitrides, which produce internal notches in the material and have a negative influence on the fatigue strength of high-strength spring steels.
- Aluminum contents greater than 0.01% also lead to the formation of Aluminum oxides and aluminum nitrides having the above-described negative fatigue properties.
- this steel material is less suitable for the tube making process, ie, drawdown reduction, and is expensive in view of the relatively high nickel content.
- a copper content of more than 0.2% leads to grain boundary failure during hot forming, especially if, as in the case of pipe production, there are existing high stresses in hot working.
- the surface quality plays an important role.
- the improvement in surface quality can be achieved with seamless pipes by internal peeling, i. be achieved by a machining, but which is associated with high costs and thus has a low cost.
- the state of the art is still the EP 1 029 720 A2 to call.
- This relates to a method for producing a hollow stabilizer, which can be used in a vehicle, for example in a car.
- the manufacturing method described therein includes a manufacturing step of subjecting a seam-welded pipe to continuous hot working to obtain a primary pipe, and winding the primary pipe in a band ring. This is followed by a cold drawing step to obtain a pipe with a wall thickness ratio of 0.2 to 0.27 and a tensile strength of 800 to 1,000 MPa.
- a bending step the thick-walled pipe obtained by the cold-drawing step is bent in a cold state into the desired stabilizer shape. It is desirable that the carbon content of the seam-welded pipe is between 0.17 and 0.4% by weight.
- the state of the art also includes the EP 1 698 712 A1 relating to a steel for a high strength spring, which contains 0.35% to 0.65% carbon, 1.4% to 2.5% silicon, 0.1% to 1.0% manganese, up to 2.0% chromium up to 1.0% nickel, up to 1.0% copper, up to 0.02% phosphorus, up to 0.02% sulfur, up to 0.006% nitrogen and up to 0.1% aluminum, balance iron and contains unavoidable impurities.
- This steel has a good cold workability.
- the invention is based on the object to show the use of a steel alloy as a material for the production of dynamically loaded pipe components, the material meets the high requirements for the production of dynamically loaded tubular components, in particular for the production of straight or tortuous torsion springs, such.
- Coil springs, or hollow shafts is suitable and also reached the strength level of spring steels.
- the tensile strength of the pipe component produced from this material is in the tempered state in a range greater than 1,800 MPa, wherein the yield strength Rp02 is in a range greater than 1,600 MPa.
- This material is ideal for the production of stabilizers, drive shafts, torsion bars and coil springs, ie generally for straight or tortuous torsion springs and hollow shafts that are dynamically stressed. These favorable material properties have led to a variation of the chemical compositions by lowering the carbon content and an optimization of the Cr-Si-Mn balance and the use of a microalloying concept (Nb, V, B).
- the material can withstand very high cooling rates and can therefore be quenched with quenching rates of greater than 200 K / s without causing any crazing or significant distortion.
- Conventional spring steels are hardened in oil at much slower cooling rates ( ⁇ 100 K / s).
- the steel material is still weldable even if the carbon content is greater than 0.35%, so that as a production method for dynamically loaded Pipe components a) both welding and drawing, b) direct welding, and c) are suitable for seamless production.
- the good weldability is achieved by a comparatively high ductility in the weld area, so that a reduced tendency for brittle failure of the weld during cooling and when calibrating the tubes is present.
- This can be attributed to the finest lamellae made of retained austenite in the hardened structure. In the transmission electron microscope, these lamellae become visible in the nanometer range. These fins increase the ductility of the hardness structure without lowering the yield strength and strength.
- the lamellae have a mean particle size of 60-70 nm.
- a seamless production is particularly suitable in combination with an optimized internal machining, if the wall thickness s in a range greater than 18% of the outer diameter D is (s / D> 18%).
- the material according to the invention is therefore suitable for all tube production methods mentioned above, is also inexpensive to produce and has the potential due to high achievable strength values, for torsionally loaded components, e.g. Torsion springs to replace solid materials.
- the pipe component produced has an elongation A5 greater than 9%. It is also noteworthy that even at a very low tempering temperature of 250 C, a fracture constriction Z of greater than 30% is achieved, so that a high yield strength is maintained.
- the quenching takes place by preferably inductive heating to Austenitmaschinestemperatur from 900 to 950 ° C, followed by quenching in water or oil (preferably water at a cooling rate> 200 K / s, in particular> 400 K / s) and then tempering to a temperature of 200 300 ° C, preferably ⁇ 275 ° C, in particular to a temperature of 250 ° C.
- water or oil preferably water at a cooling rate> 200 K / s, in particular> 400 K / s
- dynamic loadable pipe components in diameter ranges from 3mm to 150 mm, in particular in Make diameter ranges from 8 mm to 50 mm.
- the wall thickness is preferably 10% to 22% of the outer diameter of the pipe component in such dynamically loaded pipe components.
- the production of the pipe components is preferably carried out in soft annealed, pearlitic state.
- the steel alloy no. 1 is the material as it is to be used in the pipe components according to the invention.
- the comparison material no. 2 corresponds to the alloy 34MnB5.
- the comparison material no. 3 corresponds to the alloy 25MnB5.
- the comparison material no. 4 corresponds to the alloy 42CrMo4.
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- Materials Engineering (AREA)
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Abstract
Description
Die Erfindung betrifft die Verwendung einer Stahllegierung als Werkstoff zur Herstellung von dynamisch belasteten Rohrbauteilen sowie ein solches Rohrbauteil.The invention relates to the use of a steel alloy as a material for the production of dynamically loaded pipe components and such a pipe component.
Bauteile, die über sehr lange Zeiträume hohen dynamischen Beanspruchungen standhalten müssen, sind insbesondere im Bereich des Fahrwerks von Kraftfahrzeugen zu finden. Als Beispiel sind Stabilisatoren zu nennen, welche zur Verringerung der Kurvenneigung der Karosserie und zur Beeinflussung des Eigenlenkverhaltens eingesetzt werden. Sie versteifen bei einseitiger Belastung die Federung, da die Widerstandskraft des Werkstoffs des Stabilisators der Seitenneigung federnd entgegenwirkt. Ein weiteres Beispiel wäre eine torsionsbelastete Welle.Components that have to withstand high dynamic loads for very long periods of time can be found particularly in the area of the chassis of motor vehicles. As an example, stabilizers should be mentioned which are used to reduce the tendency of the body to curve and to influence the self-steering behavior. They stiffen the suspension in one-sided load, since the resistance of the material of the stabilizer of the side slope resiliently counteracts. Another example would be a torsionally loaded shaft.
Stabilisatoren sind hinsichtlich der Beanspruchungsart geraden Torsionsfedern oder auch Drehstäben zuzuordnen, da ein Stabilisator bei unterschiedlichem Einfedern der Räder um seine Längsachse verdrillt wird. Aus der
Ein weiterer wesentlicher Faktor zur Erzielung einer hohen Dauerwechselfestigkeit ist die Oberflächengüte der Außen- und Innenoberfläche der verwendeten Rohre. Die besten Oberflächengüten weisen längsnahtgeschweißte und ggf. nachfolgend kalt gezogene Rohre aus gewalztem Stahlband auf. Hierbei werden die bei nahtlos gezogenen Rohren vorkommenden Fehler, wie Fältelungen usw., vermieden.Another essential factor for achieving a high permanent fatigue strength is the surface quality of the outer and inner surface of the tubes used. The best surface qualities have longitudinally welded and possibly subsequently cold drawn tubes made of rolled steel strip. In this case, the errors occurring in seamless drawn pipes, such as pleats, etc., avoided.
Der in der
Zum Stand der Technik zählt auch die
Die ebenfalls bekannten höchstfesten Federstähle 50CrV4, 55SiCr6 sind schweißtechnisch nicht zu verarbeiten und damit zur Herstellung von geschweißten und nachgezogenen Rohren nicht geeignet.The also known high-strength spring steels 50CrV4, 55SiCr6 are not technically weldable and therefore not suitable for the production of welded and redrawn tubes.
Stand der Technik ist nach Kenntnis der Anmelderin die Herstellung von geschweißten Rohren durch Press-Schweißverfahren bis zu einem Kohlenstoff Gehalt von ca. 0,35 %. Ein höherer Kohlenstoffgehalt führt in der Regel zu hohen Spitzenhärten in der Schweißnaht mit derart verringerter Duktilität, dass während der Kalibrierung und Abkühlung des Rohrbauteils Risse entstehen. Daher gelten Stähle mit Kohlenstoff-Gehalten über 0,35 % allgemein als nicht schweißbar.To the knowledge of the Applicant, the state of the art is the production of welded tubes by press-welding processes up to a carbon content of about 0.35%. A higher carbon content typically results in high peak hardness in the weld with such reduced ductility that cracks occur during calibration and cooling of the pipe component. Therefore, steels with carbon contents above 0.35% are generally considered non-weldable.
Wenn aufgrund eines hohen Kohlenstoffgehaltes nahtlos gezogene Stahlrohre zum Einsatz kommen sollen, spielt die Oberflächenqualität eine wichtige Rolle. Die Verbesserung der Oberflächenqualität kann bei nahtlosen Rohren durch Innenschälen, d.h. durch eine spanabhebende Bearbeitung, erreicht werden, die allerdings mit hohen Kosten verbunden ist und damit nur eine geringe Wirtschaftlichkeit aufweist.If, due to a high carbon content, seamlessly drawn steel tubes are to be used, the surface quality plays an important role. The improvement in surface quality can be achieved with seamless pipes by internal peeling, i. be achieved by a machining, but which is associated with high costs and thus has a low cost.
Aufgrund der Tatsache, dass die Festigkeit von geeigneten Rohrwerkstoffen bislang auf ca. 1.800 MPa begrenzt war und im Bereich der Vollmaterialien Festigkeiten in einer Größenordnung von 2.100 MPa realisiert werden konnten, wie z.B. in der Fedemindustrie bei der Verwendung von 55SiCr6, war es bislang nicht möglich, das Leichtbaupotenzial von dynamisch belasteten Rohrbauteilen vollständig auszunutzen.Due to the fact that the strength of suitable pipe materials was previously limited to about 1,800 MPa and could be realized in the range of solid materials strengths in the order of 2,100 MPa, such as in the Fedemindustrie with the use of 55SiCr6, it was not possible to make full use of the lightweight construction potential of dynamically loaded pipe components.
Zum Stand der Technik ist noch die
Zum Stand der Technik zählt auch die
Der Erfindung liegt hiervon ausgehend die Aufgabe zugrunde, die Verwendung einer Stahllegierung als Werkstoff zur Herstellung von dynamisch belasteten Rohrbauteilen aufzuzeigen, wobei der Werkstoff den hohen Anforderungen für die Herstellung von dynamisch belasteten Rohrbauteilen, insbesondere zur Herstellung von geraden oder gewundenen Torsionsfedern, wie z.B. Schraubenfedern, oder auch Hohlwellen geeignet ist und zudem das Festigkeitsniveau von Federstählen erreicht.The invention is based on the object to show the use of a steel alloy as a material for the production of dynamically loaded pipe components, the material meets the high requirements for the production of dynamically loaded tubular components, in particular for the production of straight or tortuous torsion springs, such. Coil springs, or hollow shafts is suitable and also reached the strength level of spring steels.
Diese Aufgabe wird durch die Merkmale des Patentanspruchs 1 gelöst.This object is solved by the features of patent claim 1.
Vorteilhafte Weiterbildungen des Erfindungsgedankens sind Gegenstand der Unteransprüche. Ein Rohrbauteil mit den gewünschten Eigenschaften ist Gegenstand des Patentanspruchs 5.Advantageous developments of the inventive concept are the subject of the dependent claims. A pipe component with the desired properties is the subject of patent claim 5.
Die Lösung des vorstehend beschriebenen Problems wird in der Verwendung einer Stahllegierung als Werkstoff zur Herstellung von dynamisch belasteten Rohrbauteilen gesehen, wobei die Stahllegierung in Gewichtsprozenten aus
Der Stahlwerkstoff ist auch dann noch schweißbar, wenn der Kohlenstoffgehalt größer als 0,35 % ist, so dass sich als Herstellungsverfahren für dynamisch belastete Rohrbauteile a) sowohl das Schweißen und Ziehen, b) das direkte Schweißen, als auch c) die nahtlose Herstellung eignen.The steel material is still weldable even if the carbon content is greater than 0.35%, so that as a production method for dynamically loaded Pipe components a) both welding and drawing, b) direct welding, and c) are suitable for seamless production.
Die gute Schweißbarkeit wird durch eine vergleichsweise hohe Duktilität im Schweißnahtbereich erreicht, so dass eine verminderte Neigung zum spröden Versagen der Schweißnaht bei der Abkühlung und beim Kalibrieren der Rohre vorhanden ist. Dies kann auf feinste Lamellen aus Restaustenit im Härtegefüge zurückgeführt werden. Im Transmissionselektronenmikroskop werden diese Lamellen im Nanometerbereich sichtbar. Diese Lamellen erhöhen die Duktilität des Härtegefüges ohne die Streckgrenze und Festigkeit abzusenken. Die Lamellen besitzen eine mittlere Korngröße von 60 - 70 nm.The good weldability is achieved by a comparatively high ductility in the weld area, so that a reduced tendency for brittle failure of the weld during cooling and when calibrating the tubes is present. This can be attributed to the finest lamellae made of retained austenite in the hardened structure. In the transmission electron microscope, these lamellae become visible in the nanometer range. These fins increase the ductility of the hardness structure without lowering the yield strength and strength. The lamellae have a mean particle size of 60-70 nm.
Eine nahtlose Herstellung bietet sich insbesondere in Kombination mit einer optimierten Innenbearbeitung an, wenn die Wanddicke s in einem Bereich größer als 18 % des Außendurchmessers D ist (s/D > 18 %). Der erfindungsgemäße Werkstoff eignet sich daher für alle genannten Rohrherstellungsverfahren, ist zudem kostengünstig herstellbar und besitzt aufgrund hoher erreichbarer Festigkeitswerte das Potenzial, bei torsionsbelasteten Bauteilen, z.B. Torsionsfedern, Vollmaterialien zu ersetzen.A seamless production is particularly suitable in combination with an optimized internal machining, if the wall thickness s in a range greater than 18% of the outer diameter D is (s / D> 18%). The material according to the invention is therefore suitable for all tube production methods mentioned above, is also inexpensive to produce and has the potential due to high achievable strength values, for torsionally loaded components, e.g. Torsion springs to replace solid materials.
Im vergüteten Zustand ist es möglich, mit den zuvor genannten Legierungen Zugfestigkeiten Rm größer als 2.000 MPa und Streckgrenzen Rp0,2 größer als 1.900 MPa zu erreichen. Im vergüteten Zustand besitzt das hergestellte Rohrbauteil eine Dehnung A5 größer als 9 %. Bemerkenswert ist zudem, dass bereits bei einer sehr niedrigen Anlasstemperatur von 250 C eine Brucheinschnürung Z von größer als 30 % erreicht wird, so dass eine hohe Streckgrenze erhalten bleibt.In the tempered state, it is possible to achieve with the aforementioned alloys tensile strengths Rm greater than 2,000 MPa and yield strengths Rp0,2 greater than 1,900 MPa. In the tempered state, the pipe component produced has an elongation A5 greater than 9%. It is also noteworthy that even at a very low tempering temperature of 250 C, a fracture constriction Z of greater than 30% is achieved, so that a high yield strength is maintained.
Das Vergüten erfolgt durch vorzugsweise induktives Aufheizen auf Austenitisierungstemperatur von 900 - 950 °C, anschließendes Abschrecken in Wasser oder Öl (vorzugsweise Wasser mit einer Abkühlgeschwindigkeit > 200 K/s, insbesondere > 400 K/s) und anschließendes Anlassen auf eine Temperatur von 200 - 300 °C, vorzugsweise < 275 °C, insbesondere auf eine Temperatur von 250 °C.The quenching takes place by preferably inductive heating to Austenitisierungstemperatur from 900 to 950 ° C, followed by quenching in water or oil (preferably water at a cooling rate> 200 K / s, in particular> 400 K / s) and then tempering to a temperature of 200 300 ° C, preferably <275 ° C, in particular to a temperature of 250 ° C.
Auf diese Weise lassen sich dynamisch belastbare Rohrbauteile in Durchmesserbereichen von 3mm bis 150 mm, insbesondere in Durchmesserbereichen von 8 mm bis 50 mm herstellen. Die Wanddicke beträgt bei derart dynamisch belasteten Rohrbauteilen vorzugsweise 10 % bis 22 % des Außendurchmessers des Rohrbauteils. Die Herstellung der Rohrbauteile erfolgt bevorzugt im weichgeglühten, perlitischen Zustand.In this way, dynamic loadable pipe components in diameter ranges from 3mm to 150 mm, in particular in Make diameter ranges from 8 mm to 50 mm. The wall thickness is preferably 10% to 22% of the outer diameter of the pipe component in such dynamically loaded pipe components. The production of the pipe components is preferably carried out in soft annealed, pearlitic state.
Durch die Verwendung der erfindungsgemäßen Legierung kann aufgrund der höheren Werkstofffestigkeiten eine Gewichtsreduktion größer als 20 % im Verhältnis zu vergleichbaren Bauteilen aus Vollmaterial erreicht werden. Zudem führt die geringere Masse zu einer vorteilhaften Erhöhung der Eigenfrequenzen der dynamisch belasteten Rohrbauteile. Ein weiterer Vorteil ist, dass dieser hochbelastbare Federstahl wasservergütbar ist.By using the alloy according to the invention, a weight reduction greater than 20% in relation to comparable components made of solid material can be achieved due to the higher material strengths. In addition, the lower mass leads to an advantageous increase in the natural frequencies of the dynamically loaded pipe components. Another advantage is that this heavy-duty spring steel is water-resistant.
Anhand der nachfolgenden Tabelle wird deutlich, welche hervorragenden Eigenschaften die Stahllegierung für den beanspruchten Verwendungszweck mit sich bringt.On the basis of the following table, it becomes clear which excellent properties the steel alloy brings for the claimed use.
In der nachfolgenden Tabelle sind Stahllegierungen 1 bis 5 unterschiedlicher chemischer Zusammensetzung aufgelistet. Die Stahllegierung Nr. 1 ist der Werkstoff, wie er bei den erfindungsgemäßen Rohrbauteilen verwendet werden soll. Der Vergleichswerkstoff Nr. 2 entspricht der Legierung 34MnB5. Der Vergleichswerkstoff Nr. 3 entspricht der Legierung 25MnB5. Der Vergleichswerkstoff Nr. 4 entspricht der Legierung 42CrMo4. Der Vergleichswerkstoff Nr. 5 entspricht der Legierung 70Mn7. Sämtliche Stahllegierungen befinden sich im Lieferzustand QT (QT= Quenched and Tempered, d.h. gehärtet und angelassen). Sie sind mit einer Anlasstemperatur von 250 °C vergütet worden. Es fällt auf, dass die Zugfestigkeit Rm bei der Stahllegierung Nr. 1 mit einem aus dem Wertebereich 2.138 MPa bis 2.152 MPa arithmetische gemittelten Wert für die Festigkeit Rm von 2.145 MPa Werte größer als 2.100 MPa erreicht. Dabei ist der aus dem Wertebereich von 2.072 MPa bis 2.085 MPa arithmetisch gemittelte Wert für die die Streckgrenze Rp0,2 mit 2.078 MPa größer als 2.000 MPa. Gleichzeitig liegt die Bruchdehnung A5 mit Werten von 9,3% bis 9.8% (arithmetisch gemittelt 9,5%) deutlich über den Werten der Vergleichswerkstoffe. Auch die Brucheinschnürung Z liegt mit Werten von 30,3 % bis 32,6 % (arithmetisch gemittelt 31,5 %) höher als die Brucheinschnürungen der Vergleichsproben.
Claims (13)
- Use of a steel alloy as a material for producing dynamically loaded tube components, which consists, in per cent by weight, of
carbon 0.40 - 0.44 silicon 1.5 - 2.2 manganese 0.3 - 0.8 chromium 1.1 - 1.5 nitrogen 0.004 - 0.015 niobium 0.02 - 0.04 vanadium 0.01 - 0.015 boron 0.002 - 0.004, - Use of a steel alloy according to claim 1, characterized in that in a tempered condition of the tube component the tensile strength Rm is higher than 2,000 MPa and the yield point Rp0.2 is higher than 1,900 MPa.
- Use of a steel alloy according to claim 1, characterized in that in a tempered condition of the tube component the tensile strength Rm is higher than 2,100 MPa and the yield point Rp0.2 is higher than 2,000 MPa.
- Use of a steel alloy according to any one of claims 1 to 3, characterized in that in a tempered condition of the tube component the expansion A5 is higher than 9%.
- A tube component made of a steel alloy which, in per cent by weight, consists of 0.40 - 0.44 of carbon, 1.5 - 2.2 of silicon, 0.3 - 0.8 of manganese, 1.1 - 1.5 of chromium, 0.004 - 0.015 of nitrogen, 0.02 - 0.04 of niobium, 0.01 - 0.015 of vanadium, 0.002 - 0.004 of boron, the balance is comprised of iron and usual impurities, wherein a maximum of 0.015% of phosphorus, a maximum of 0.01% of sulphur, a maximum of 0.2% of nickel, a maximum of 0.1 % of copper, a maximum of 0.02% of tin, a maximum of 0.015% of aluminium, a maximum of 0.01 % of titanium, a maximum of 0.08% of molybdenum are among the usual impurities, and wherein the tensile strength Rm of the tube component in a tempered condition is higher than 1,800 MPa and the yield point Rp0.2 is higher than 1,600 MPa, characterized in that it is water-quenched with a quenching speed of more than 200 Kelvin/second and subsequently tempered to a temperature of 200 - 300°C.
- The tube component made of a steel alloy according to any one of claims 1 to 4, characterized in that at a tempering temperature of 250°C the per cent area reduction at fracture Z is higher than 30%.
- The tube component made of a steel alloy according to any one of claims 1 to 4, characterized in that the outer diameter thereof is in a range of 3 mm to 150 mm.
- The tube component according to claim 7, characterized in that the outer diameter is in a range of 8 mm to 50 mm.
- The tube component according to claim 7 or 8, characterized in that its wall thickness is between 10% and 25% of its outer diameter.
- The tube component made of a steel alloy according to any one of claims 1 to 4, characterized in that it is a torque-transferring or torsionally stressed component.
- The tube component according to claim 10, characterized in that it is a straight or wound torsion spring or a hollow shaft.
- The tube component according to any one of claims 5 to 11, characterized in that the surface decarburization depth is 50 µm maximum.
- The tube component according to any one of claims 5 to 12, characterized in that the crack depth is 50 µm maximum.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102007006875A DE102007006875A1 (en) | 2007-02-07 | 2007-02-07 | Use of a steel alloy containing alloying additions of carbon, silicon, manganese, chromium, niobium and boron as a material in the production of dynamically loaded tubular components |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1961832A1 EP1961832A1 (en) | 2008-08-27 |
EP1961832B1 true EP1961832B1 (en) | 2011-11-30 |
Family
ID=39204871
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP08002285A Not-in-force EP1961832B1 (en) | 2007-02-07 | 2008-02-07 | Use of a steel alloy as a substance for producing dynamically loaded tube components and tube component |
Country Status (3)
Country | Link |
---|---|
EP (1) | EP1961832B1 (en) |
AT (1) | ATE535625T1 (en) |
DE (1) | DE102007006875A1 (en) |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102012111679A1 (en) | 2012-01-19 | 2013-07-25 | Gesenkschmiede Schneider Gmbh | Low-alloy steel and components manufactured using it |
JP2018538440A (en) * | 2015-11-16 | 2018-12-27 | ベントラー スティール / チューブ ゲーエムベーハー | Alloy steel and pipe products with high energy absorption capability |
DE102016108836B4 (en) | 2016-05-12 | 2018-05-24 | Benteler Automobiltechnik Gmbh | Motor vehicle component and method for its production |
Family Cites Families (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE2917287C2 (en) * | 1978-04-28 | 1986-02-27 | Neturen Co. Ltd., Tokio/Tokyo | Process for the manufacture of coil springs, torsion bars or the like from spring steel wire |
US4533402A (en) * | 1984-02-16 | 1985-08-06 | Nhk Spring Co., Ltd. | Method of manufacturing a hollow stabilizer |
US5236520A (en) * | 1990-10-24 | 1993-08-17 | Consolidated Metal Products, Inc. | High strength steel sway bars and method of making |
DE4321241A1 (en) * | 1993-06-25 | 1995-01-05 | Hesonwerk Dr Iske Gmbh | Use of steel pipes or bars for manufacturing chassis stabilisers for motor vehicles |
DE4440729C2 (en) * | 1994-11-15 | 1999-07-29 | Datec Scherdel Gmbh | Relaxation-resistant steel spring |
EP0753595B1 (en) | 1995-07-06 | 2001-08-08 | Benteler Ag | Pipes for manufacturing stabilisers and manufacturing stabilisers therefrom |
KR100353322B1 (en) * | 1998-06-23 | 2002-09-18 | 스미토모 긴조쿠 고교 가부시키가이샤 | Steel Wire Rod and Process for Producing Steel for Steel Wire Rod |
JP4331300B2 (en) | 1999-02-15 | 2009-09-16 | 日本発條株式会社 | Method for manufacturing hollow stabilizer |
CA2340688A1 (en) * | 1999-06-16 | 2000-12-21 | Nippon Steel Corporation | Super-clean steel |
US6447622B1 (en) * | 1999-06-16 | 2002-09-10 | Nippon Steel Corporation | High carbon steel wire excellent in wire-drawability and in fatigue resistance after wire drawing |
JP2001355047A (en) * | 2000-06-14 | 2001-12-25 | Kawasaki Steel Corp | High carbon steel tube excellent in cold workability and induction hardenability and its production method |
KR100514120B1 (en) * | 2000-12-20 | 2005-09-13 | 신닛뽄세이테쯔 카부시키카이샤 | High-strength spring steel and spring steel wire |
JP4044460B2 (en) * | 2003-02-28 | 2008-02-06 | 大同特殊鋼株式会社 | Cold forming spring steel |
DE102004053620A1 (en) * | 2004-11-03 | 2006-05-04 | Salzgitter Flachstahl Gmbh | High-strength, air-hardening steel with excellent forming properties |
JP4476846B2 (en) | 2005-03-03 | 2010-06-09 | 株式会社神戸製鋼所 | High strength spring steel with excellent cold workability and quality stability |
-
2007
- 2007-02-07 DE DE102007006875A patent/DE102007006875A1/en not_active Ceased
-
2008
- 2008-02-07 EP EP08002285A patent/EP1961832B1/en not_active Not-in-force
- 2008-02-07 AT AT08002285T patent/ATE535625T1/en active
Also Published As
Publication number | Publication date |
---|---|
EP1961832A1 (en) | 2008-08-27 |
ATE535625T1 (en) | 2011-12-15 |
DE102007006875A1 (en) | 2008-08-14 |
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