EP1961832B1 - Utilisation d'un alliage d'acier en tant que matière première pour la fabrication de composants de tuyaux chargés dynamiquement et composant de tuyau - Google Patents
Utilisation d'un alliage d'acier en tant que matière première pour la fabrication de composants de tuyaux chargés dynamiquement et composant de tuyau Download PDFInfo
- Publication number
- 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
- Authority
- EP
- European Patent Office
- Prior art keywords
- maximum
- tube component
- mpa
- steel alloy
- tube
- 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.)
- Not-in-force
Links
Classifications
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
-
- 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
-
- 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.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Claims (13)
- Utilisation d'un alliage d'acier en tant que matériau pour la réalisation d'éléments tubulaires soumis à des sollicitations dynamiques, lequel contient en pourcentages en poids du
carbone 0,40 - 0,44 silicium 1,5 - 2,2 manganèse 0,3 - 0,8 chrome 1,1 - 1,5 azote 0,004 - 0,015 niobium 0,02 - 0,04 vanadium 0,01 - 0,015 bore 0,002 - 0,004 - Utilisation d'un alliage d'acier selon la revendication 1, caractérisée en ce que l'élément tubulaire à l'état trempé et revenu a une résistance à la traction Rm supérieure à 2 000 MPa et une limite d'élasticité Rp0,2 supérieure à 1 900 MPa.
- Utilisation d'un alliage d'acier selon la revendication 1, caractérisée en ce que l'élément tubulaire à l'état trempé et revenu a une résistance à la traction Rm supérieure à 2 100 MPa et une limite d'élasticité Rp0,2 supérieure à 2 000 MPa.
- Utilisation d'un alliage d'acier selon l'une quelconque des revendications 1 à 3, caractérisée en ce que l'allongement A5 de l'élément tubulaire à l'état trempé et revenu est supérieur à 9 %.
- Élément tubulaire réalisé à partir d'un alliage d'acier qui contient en pourcentages en poids du carbone 0,40 - 0,44, du silicium 1,5 - 2,2, du manganèse 0,3 - 0,8, du chrome 1,1 - 1,5, de l'azote 0,004 - 0,015, du niobium 0,02 - 0,04, du vanadium 0,01 - 0,015, du bore 0,002 - 0,004, du fer et des impuretés usuelles pour le reste, sachant que parmi les impuretés usuelles figurent 0,015 % maximum de phosphore, 0,01 % maximum de soufre, 0,2 % maximum de nickel, 0,1 % maximum de cuivre, 0,02 % maximum d'étain, 0,015 % maximum d'aluminium, 0,01 % maximum de titane, 0,08 % maximum de molybdène, et sachant que la résistance à la traction Rm de l'élément tubulaire à l'état trempé et revenu est supérieure à 1 800 MPa et la limite d'élasticité Rp0,2 est supérieure à 1 600 MPa, caractérisé en ce qu'il subit une trempe à l'eau avec une vitesse de trempe supérieure à 200 Kelvin/seconde et est revenu ensuite à une température de 200 à 300°C.
- Élément tubulaire réalisé à partir d'un alliage d'acier selon l'une quelconque des revendications 1 à 4, caractérisé en ce qu'en présence d'une température de revenu de 250°C, la striction Z est supérieure à 30 %.
- Élément tubulaire réalisé à partir d'un alliage d'acier selon l'une quelconque des revendications 1 à 4, caractérisé en ce que son diamètre extérieur se situe dans une plage de 3 mm à 150 mm.
- Élément tubulaire selon la revendication 7, caractérisé en ce que le diamètre extérieur se situe dans une plage de 8 mm à 50 mm.
- Élément tubulaire selon la revendication 7 ou 8, caractérisé en ce que son épaisseur de paroi se situe entre 10 % et 25 % de son diamètre extérieur.
- Élément tubulaire réalisé à partir d'un alliage d'acier selon l'une quelconque des revendications 1 à 4, caractérisé en ce qu'il s'agit d'un élément de construction transmettant un couple de rotation ou sollicité en torsion.
- Élément tubulaire selon la revendication 10, caractérisé en ce qu'il s'agit d'une barre de torsion droite ou en spirale ou d'un arbre creux.
- Élément tubulaire selon l'une quelconque des revendications 5 à 11, caractérisé en ce que la décarburation superficielle est de l'ordre de 50 µm maximum.
- Élément tubulaire selon l'une quelconque des revendications 5 à 12, caractérisé en ce que la profondeur de défaut est de l'ordre de 50 µm maximum.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102007006875A DE102007006875A1 (de) | 2007-02-07 | 2007-02-07 | Verwendung einer Stahllegierung als Werkstoff zur Herstellung von dynamisch belasteten Rohrbauteilen und Rohrbauteil |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1961832A1 EP1961832A1 (fr) | 2008-08-27 |
EP1961832B1 true EP1961832B1 (fr) | 2011-11-30 |
Family
ID=39204871
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP08002285A Not-in-force EP1961832B1 (fr) | 2007-02-07 | 2008-02-07 | Utilisation d'un alliage d'acier en tant que matière première pour la fabrication de composants de tuyaux chargés dynamiquement et composant de tuyau |
Country Status (3)
Country | Link |
---|---|
EP (1) | EP1961832B1 (fr) |
AT (1) | ATE535625T1 (fr) |
DE (1) | DE102007006875A1 (fr) |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102012111679A1 (de) * | 2012-01-19 | 2013-07-25 | Gesenkschmiede Schneider Gmbh | Niedrig legierter Stahl und damit hergestellte Bauteile |
CN108474080B (zh) * | 2015-11-16 | 2021-09-21 | 本特勒尔钢管有限公司 | 具有高能量吸收能力的钢合金和钢管产品 |
DE102016108836B4 (de) | 2016-05-12 | 2018-05-24 | Benteler Automobiltechnik Gmbh | Kraftfahrzeugbauteil sowie Verfahren zu dessen Herstellung |
Family Cites Families (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2424324B1 (fr) * | 1978-04-28 | 1986-02-28 | Neturen Co Ltd | Acier pour faconnage plastique a froid et traitement thermique favorisant cette deformation |
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 (de) * | 1993-06-25 | 1995-01-05 | Hesonwerk Dr Iske Gmbh | Verwendung von Stahlrohren oder Stahlstäben zur Herstellung von Fahrwerksstabilisatoren für Kraftfahrzeuge |
DE4440729C2 (de) * | 1994-11-15 | 1999-07-29 | Datec Scherdel Gmbh | Relaxationsfeste Stahlfeder |
DE59607441D1 (de) | 1995-07-06 | 2001-09-13 | Benteler Werke Ag | Rohre für die Herstellung von Stabilisatoren und Herstellung von Stabilisatoren aus solchen Rohren |
EP1018565A4 (fr) * | 1998-06-23 | 2003-07-23 | Sumitomo Metal Ind | Tige en fil d'acier et procede de fabrication de l'acier destine a ce fil |
JP4331300B2 (ja) | 1999-02-15 | 2009-09-16 | 日本発條株式会社 | 中空スタビライザの製造方法 |
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 |
BR0006880A (pt) * | 1999-06-16 | 2001-08-07 | Nippon Steel Corp | Aço superlimpo |
JP2001355047A (ja) * | 2000-06-14 | 2001-12-25 | Kawasaki Steel Corp | 冷間加工性と高周波焼入れ性に優れた高炭素鋼管およびその製造方法 |
US7789974B2 (en) * | 2000-12-20 | 2010-09-07 | Nippon Steel Corporation | High-strength spring steel wire |
JP4044460B2 (ja) * | 2003-02-28 | 2008-02-06 | 大同特殊鋼株式会社 | 冷間成形ばね用鋼 |
DE102004053620A1 (de) * | 2004-11-03 | 2006-05-04 | Salzgitter Flachstahl Gmbh | Hochfester, lufthärtender Stahl mit ausgezeichneten Umformeigenschaften |
JP4476846B2 (ja) | 2005-03-03 | 2010-06-09 | 株式会社神戸製鋼所 | 冷間加工性と品質安定性に優れた高強度ばね用鋼 |
-
2007
- 2007-02-07 DE DE102007006875A patent/DE102007006875A1/de not_active Ceased
-
2008
- 2008-02-07 AT AT08002285T patent/ATE535625T1/de active
- 2008-02-07 EP EP08002285A patent/EP1961832B1/fr not_active Not-in-force
Also Published As
Publication number | Publication date |
---|---|
DE102007006875A1 (de) | 2008-08-14 |
EP1961832A1 (fr) | 2008-08-27 |
ATE535625T1 (de) | 2011-12-15 |
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