EP1966407B1 - Federstahl, verfahren zur herstellung einer feder aus diesem stahl und eine feder aus diesem stahl - Google Patents

Federstahl, verfahren zur herstellung einer feder aus diesem stahl und eine feder aus diesem stahl Download PDF

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EP1966407B1
EP1966407B1 EP06841905A EP06841905A EP1966407B1 EP 1966407 B1 EP1966407 B1 EP 1966407B1 EP 06841905 A EP06841905 A EP 06841905A EP 06841905 A EP06841905 A EP 06841905A EP 1966407 B1 EP1966407 B1 EP 1966407B1
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Prior art keywords
steel
traces
spring
fatigue
hardness
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EP1966407A1 (de
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Nao Yoshihara
Kazuhisa Kawata
Julie Mougin
Jacques Languillaume
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Ascometal SA
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Ascometal SA
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Priority to MEP-2009-344A priority Critical patent/ME01062B/me
Priority to SI200630437T priority patent/SI1966407T1/sl
Priority to PL06841905T priority patent/PL1966407T3/pl
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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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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

Definitions

  • the invention relates to iron and steel, and more specifically to the field of spring steels.
  • the documents FR-A-2,740,476 and JP-A-3,474,373 disclose a spring steel grade having good resistance to hydrogen embrittlement and good fatigue strength, wherein carbonitrosulfide inclusions comprising at least one of titanium, niobium, zirconium, tantalum or hafnium, are controlled to have a small average size, less than 5 ⁇ m in diameter, and to be very large (10,000 or more on a section of cut).
  • JP 09324219 A discloses a Cr, Ni, V, Cu, Ti and Nb spring steel grade having resistance to hydrogen embrittlement, a resistance greater than 2000 MPa and a hardness greater than 50 HRC.
  • this type of steel leads, after quenching and tempering according to the industrial process of manufacturing springs, to a hardness level of only 50HRC or a little more, corresponding to a tensile strength of 1700 MPa or a little more , but hardly greater than 1900MPa, corresponding to a hardness of 53.5HRC. Because of this moderate hardness level, this steel has only moderate scuff resistance, and steel with higher tensile strength is required to improve the scuff resistance. Thus, such a steel does not provide an excellent compromise between a high strength, which would be greater than 2100MPa, a hardness that would be greater than 55HRC, a high resistance to fatigue in the air and a resistance to fatigue under corrosion. less equivalent, and even superior, to what is necessary for springs.
  • the object of the invention is to propose means for producing, simultaneously with known spring steels, an increase in the hardness and the tensile strength of the springs, the higher fatigue properties in the air, the properties in corrosion fatigue at least equivalent and even higher, a resistance to slackening of the upper spring and less sensitivity to surface defects that can be generated during the twisting of the spring.
  • the maximum size of Ti nitrides or carbonitrides observed at 1.5 ⁇ 0.5mm from the surface of a bar, wire rod, slug or spring over 100mm 2 of the cutting surface is preferably less than or equal to 20 .mu.m, said size being the square root of the surface of inclusions considered as squares.
  • the invention also relates to springs made of such steel, and springs made of a steel obtained by the above method.
  • a steel having the above-mentioned characteristics of inclusionary composition and morphology made it possible, after elaboration, casting, rolling, quenching and tempering, to obtain, under specific conditions, a hardness greater than 55HRC, while achieving an excellent compromise between a long fatigue life in the air and fatigue under corrosion, a high resistance to cyclic sagging and a low sensitivity to surface defects occurring during the manufacture of the spring.
  • composition of the steel according to the invention must meet the following requirements.
  • the carbon content must be between 0.45 and 0.7%. Carbon, after quenching and tempering, increases the tensile strength and hardness of steel. If the carbon content is less than 0.45%, in the temperature range usually used for the manufacture of the springs, no quenching and tempering treatment leads to a high strength and high hardness of the steel described in the invention. On the other hand, if the carbon content exceeds 0.7% or even 0.65%, coarse and very hard carbides combined with chromium, molybdenum and vanadium may remain undissolved during austenitization performed prior to quenching, and can significantly affect fatigue life in air, fatigue resistance under corrosion and also toughness. As a result carbon contents above 0.7% are to be excluded. Preferably, they should not exceed 0.65%.
  • the silicon content is between 1.65 and 2.5%. Silicon is an important element for ensuring, thanks to its presence in solid solution, high levels of strength and hardness, as well as high Ceq equivalent carbon and resistance values. To obtain the values of tensile strength and hardness of the steel according to the invention, the Silicon content should not be lower than 1.65%. In addition, silicon contributes at least partially to the deoxidation of the steel. If its content exceeds 2.5% or even 2.2%, the oxygen content of the steel may be, by thermodynamic reaction, greater than 0.0020 or even 0.0025%. This reflects the formation of oxides of various compositions that are detrimental to the fatigue resistance in the air.
  • silicon contents greater than 2.5% segregations of various combined elements such as manganese, chromium or the like may occur during solidification after casting. These segregations are very damaging to fatigue behavior in the air and resistance to fatigue under corrosion.
  • silicon content greater than 2.5% the decarburization on the surface of the bars or wires intended to form the springs becomes too important for the properties in service of the spring. This is why the silicon content should not exceed 2.5%, and preferably 2.2%.
  • the manganese content is between 0.20 and 0.75%.
  • Manganese, in combination with residual sulfur between trace amounts and 0.015%, must be added at a level at least greater than ten times the sulfur content so as to avoid the formation of iron sulphides which are extremely damaging to the laminability of the iron. 'steel. As a result, a minimum manganese content of 0.20% is required.
  • manganese contributes to solid solution hardening during the quenching of steel, in the same way as nickel, chromium, molybdenum and vanadium, which makes it possible to obtain the values of tensile strength and high hardness and equivalent carbon Ceq values of the steel according to the invention.
  • the chromium content should be between 0.60 and 2%, and preferably between 0.80 and 1.70%. Chromium is added to obtain, in solid solution after austenitization, quenching and tempering, high values of resistance tensile strength and hardness, and to help achieve the equivalent value of carbon Ceq, but also to increase resistance to fatigue under corrosion. To ensure these properties, the chromium content should be at least 0.60%, and preferably at least 0.80%. Above 2%, or even 1.7%, particular, coarse and very hard chromium carbides, in combination with vanadium and molybdenum, may remain after the austenitization treatment performed prior to quenching. Such carbides greatly affect the fatigue resistance in the air. This is why the chromium content must not exceed 2%.
  • the nickel content is between 0.15 and 1%.
  • Nickel is added to increase the hardenability of the steel, as well as the tensile strength and hardness after quenching and tempering. As it does not form carbides, nickel contributes to the hardening of steel, just like chromium, molybdenum and vanadium, without the formation of particular coarse and hard carbides that would not be dissolved during the austenitization performed before quenching. and could be harmful to the fatigue resistance in the air. It also makes it possible to adjust the equivalent carbon between 0.8 and 1% in the steel according to the invention as necessary. As a non-oxidizable element, nickel improves fatigue resistance under corrosion. To ensure that these effects are significant, the nickel content should not be less than 0.15%.
  • nickel can lead to a too high residual austenite content, the presence of which is very damaging to the resistance to fatigue under corrosion.
  • high levels of nickel significantly increase the cost of steel. For all these reasons, the nickel content should not exceed 1%, better 0.80%
  • the molybdenum content must be between traces and 1%. Like chromium, molybdenum increases the hardenability of steel, as does its strength. In addition it has a low oxidation potential. For these two reasons, molybdenum is conducive to fatigue resistance in the air and under corrosion. But for contents higher than 1%, even 0.80%, coarse and very hard molybdenum carbides may remain, possibly combined with vanadium and chromium, after austenitization prior to quenching. These Particular carbides are very damaging to fatigue resistance in the air. Finally, addition of molybdenum exceeding 1% unnecessarily increases the cost of steel. This is why the molybdenum content should not exceed 1%, better 0.80%.
  • the vanadium content should be between 0.003 and 0.8%.
  • Vanadium is an element that increases quenchability, tensile strength and hardness after quenching and tempering.
  • vanadium makes it possible to form a large number of fine vanadium or vanadium nitrites and submicroscopic titanium to refine the grain and increase the levels of tensile strength and hardness. , thanks to a structural hardening.
  • vanadium must be present with a minimum content of 0.003%. But this element is expensive and must be kept close to this lower limit if a compromise between the cost of elaboration and the refining of the grain is sought.
  • the vanadium should not exceed 0.8% and preferably 0.5%, because above this value a precipitation of carbides containing coarse and very hard vanadium combined with chromium and molybdenum can remain in the undissolved state during the austenitization which takes place before quenching. This can be very unfavorable to the resistance to air fatigue, for the high values of strength and hardness of the steel according to the invention. And an addition of vanadium above 0.8% unnecessarily increases the cost of steel.
  • the copper content must be between 0.10 and 1%. Copper is an element that hardens steel when in solid solution after tempering and tempering treatment. Thus, it can be added with other elements contributing to increase the strength and hardness of the steel. Since it does not combine with carbon, it provides hardening of the steel without formation of hard and coarse carbides damaging the fatigue resistance in the air. From the electrochemical point of view, its passivation potential is higher than that of iron and, consequently, it is favorable to the resistance to corrosion fatigue of steel. To ensure that its effects are significant, the copper content should not be less than 0.10%. On the contrary, for contents above 1% even 0.90%, copper has a very damaging influence on the hot rolling behavior. This is why the copper content should not exceed 1%, better 0.90%.
  • the titanium content should be between 0.020 and 0.2%. Titanium is added to form, in combination with nitrogen, or even carbon and / or vanadium, fine submicroscopic nitrides or carbonitrides to refine the austenitic grain during the austenitization treatment that takes place before quenching. Thus, it increases the surface of the grain boundaries in the steel, thus leading to a reduction in the amount of unavoidable impurities segregated at grain boundaries, such as phosphorus. Such intergranular segregation would be very detrimental to toughness and fatigue resistance in the air if present at high concentrations per unit area at the grain boundaries.
  • titanium leads to the formation of other nitrides or fine carbonitrides producing an irreversible trapping effect of certain elements, such as the hydrogen formed during corrosion reactions, which can be extremely damaging to fatigue resistance under corrosion.
  • the titanium content should not be less than 0.020%.
  • above 0.2% or even 0.15% titanium can lead to the formation of coarse and hard nitrides or carbonitrides, very damaging to the resistance to fatigue in the air. This last effect is even more damaging to the high levels of tensile strength and hardness of the steel according to the invention.
  • the titanium content should not exceed 0.2%, better 0.15%.
  • niobium content must be between traces and 0.2%.
  • Niobium is added to form, in combination with carbon and nitrogen, extremely fine submicroscopic precipitates of nitrides and / or carbides and / or carbonitrides which allow, especially when the aluminum content is low (0.002% by example), to complete the refinement of the austenitic grain during the austenitization treatment performed before quenching.
  • niobium increases the surface of grain boundaries in steel, and contributes to the same favorable effect as titanium with respect to embrittlement. grain boundaries by unavoidable impurities such as phosphorus, the effect of which is very damaging to the tenacity and resistance to fatigue under corrosion.
  • niobium nitrides or carbonitrides contribute to the hardening of the steel by structural hardening.
  • the niobium content should not exceed 0.2% or even 0.15%, so that the nitrides or carbonitrides remain very thin, to ensure the refinement of the austenitic grain and avoid the formation of cracks or crevices during hot rolling.
  • the niobium content should not exceed 0.2%, better still 0.15%.
  • the aluminum content must be between 0.002 and 0.050%.
  • Aluminum can be added to complete the deoxidation of the steel and obtain oxygen levels as low as possible, and in any case less than 0.0020% in the steel according to the invention.
  • aluminum contributes to the refinement of the grain by the formation of submicroscopic nitrides.
  • an aluminum content of not less than 0.002% is required.
  • an aluminum content exceeding 0.05% can lead to the presence of large isolated inclusions or to finer but hard and angular aluminates, in the form of long strings, damaging to the fatigue life in the air and cleanliness of the steel. Therefore, the aluminum content must not exceed 0.05%.
  • the phosphorus content must be between traces and 0.015%.
  • Phosphorus is an inevitable impurity in steel.
  • elements such as chromium or manganese with the former austenitic grain boundaries. This results in a reduction of the cohesion of the grain boundaries and an intergranular embrittlement which is very damaging to the tenacity and to the resistance to fatigue in the air.
  • These effects are even more damaging to the high tensile strengths and hardness required for the steels according to the invention.
  • the phosphorus content In order to simultaneously obtain a high tensile strength and a high hardness of the spring steel and a good resistance to fatigue in the air and fatigue under corrosion, the phosphorus content must be as low as possible and should not exceed 0.015%, preferably 0.010%.
  • the sulfur content is between traces and 0.015%. Sulfur is an inevitable impurity in steels. Its content should be as low as possible, between traces and 0.015%, and preferably not more than 0.010%. It is thus desired to avoid the presence of sulfides that are unfavorable to the resistance to fatigue under corrosion and to the resistance to fatigue in the air, for the high values of strength and hardness of the steel according to the invention.
  • the oxygen content must be between traces and 0.0020%.
  • Oxygen is also an inevitable impurity in steels. Combined with deoxidizing elements, oxygen can lead to the appearance of coarse inclusions, isolated, very hard and angular, or to thinner inclusions but in the form of long chains which are very damaging to the fatigue resistance in the air. These effects are even more damaging to the high values of tensile strength and hardness of the steels according to the invention. For these reasons, in order to ensure a good compromise between high tensile strength and hardness and high resistance to fatigue in the air and fatigue under corrosion for the steel according to the invention, the oxygen content must not exceed 0.0020%.
  • the nitrogen content must be between 0.0020 and 0.0110%.
  • the nitrogen must be controlled in this range so as to form, in combination with titanium, niobium, aluminum or vanadium very fine nitrides, carbides or carbonitrides submicroscopic sufficient, allowing a grain refinement.
  • the minimum nitrogen content should be 0.0020%. Its content must not exceed 0,0110% so as to avoid the formation of coarse and hard titanium nitrides or carbonitrides greater than 20 ⁇ m, observed at 1.5 mm ⁇ 0.5 mm from the surface of the bars or wire rods used to the manufacture of springs. This location is the most critical location for fatigue loading of springs.
  • such nitrides or carbonitrides of large size are very unfavorable to the resistance to fatigue in the air for the high values of strength and hardness of the steels according to the invention, given that during fatigue tests in the air, spring break occurs at the location of such large inclusions precisely located in the vicinity of the surface of the springs as mentioned, when these inclusions are present.
  • inclusions are considered squares and their size is equal to the square root of their surface.
  • a non-limiting example of a process for producing a steel according to the invention is as follows.
  • the liquid steel is produced either in a converter or in an electric furnace and then undergoes a pocket metallurgy treatment during which alloying element additions and deoxidation are performed, and in general all secondary metallurgy operations.
  • a steel having the composition according to the invention and avoiding the formation of complex sulfides or "carbonitrosulfides" of elements such as titanium and / or niobium and / or vanadium.
  • complex sulfides or "carbonitrosulfides" of elements such as titanium and / or niobium and / or vanadium.
  • the inventors unexpectedly discovered that the contents of the various elements, in particular those of titanium, nitrogen, vanadium and sulfur, must be carefully controlled. within the aforementioned limits.
  • the steel is then cast, either by continuous casting in the form of blooms or billets, or in the form of ingots.
  • the average cooling rate of these products must be regulated in such a way that to be equal to 0.3 ° C / s or more between 1450 and 1300 ° C.
  • the products having the precise composition according to the invention are then heated and laminated between 1200 and 800 ° C in the form of machine wires, or bars in a single or double heating and rolling sequence.
  • the bars, the wires, the plots, or even the springs produced from these bars or machine wires are then subjected to a quenching treatment at the same time.
  • This quenching treatment is then followed by a tempering treatment performed specifically between 300 and 550 ° C, to obtain the high levels of tensile strength and hardness of the steel required, and to avoid on the one hand a microstructure that would lead to income fragility, and on the other hand an excessively high presence of residual austenite. It has been found that an embrittlement to the income and an excessive presence of residual austenite are extremely damaging to the resistance to corrosion fatigue of the steel according to the invention.
  • the springs are made from untreated heat bars or from machine wires or slugs from such bars, the above mentioned treatments (quenching and tempering) shall be carried out on the springs themselves under the conditions which have been said. In the case where the springs are manufactured by cold forming, these heat treatments can be conducted on the bars, or on the machine wires or slugs from these bars before the spring is made.
  • the invention makes it possible to obtain spring steels capable of reconciling a high and improved hardness and tensile strength with respect to the prior art, together with fatigue properties in the air and resistance to fatigue.
  • improved wear properties, corrosion-resistant properties at least equivalent to those of the steels known for this use, or even better, and less sensitivity to the stress concentrations produced by the surface defects that may occur during the manufacture of the spring, thanks to addition of microalloy elements, a reduction of residual elements and a control of the analysis and production chain of the steel.
  • Table 1 shows the steel compositions according to the invention and reference steels.
  • Table 1 Chemical compositions of the steels tested (in%) VS Yes mn Or Cr V Ti Cu MB Nb P S al NOT O Ceq Steel of the invention 1 0.48 1.82 0.21 0.15 1.48 0204 0072 0.20 0.02 0 0006 0006 0034 0.0051 0.0007 0.86 Steel of the invention 2 0.58 1.79 0.22 0.15 0.98 0216 0073 0.20 0.03 0 0006 0008 0032 0.0051 0.0007 0.89 Steel of the invention 3 0.59 1.80 0.22 0.15 0.99 0212 0025 0.20 0.03 0022 0007 0008 0032 0.0066 0.0008 0.91 Steel of the invention 4 0.48 2.10 0.21 0.70 1.50 0152 0069 0.51 0.03 0 0005 0005 0032 0.0042 0.0008 0.85 Steel of the invention 5 0.54 1.81 0.23 0.34 1.25 0098 0077 0.42 0.02 0 0006 0008 0031 0.0041 0.0007 0.90 Reference steel 1 0.60 1.73 0.88 0.08 0.
  • Table 2 shows the hardness values obtained for steels according to the invention and reference steels, as a function of the tempering temperature applied to them. Table 2: Hardness and tensile strength as a function of the tempering temperature. Temperature of income (° C) Hardness HRC Temperature of income (° C) Hardness HRC Steel of the invention 1 350 56.9 400 55.3 Steel of the invention 2 350 58.5 400 57.1 Steel of the invention 3 350 59.0 400 57.2 Steel of the invention 4 350 56.7 400 55.6 Steel of the invention 5 350 57.6 400 55.8 Reference steel 1 350 57.9 400 55.1 Reference steel 2 350 54.2 400 52.5 Reference steel 3 350 54.8 400 51.3
  • Table 3 shows the maximum size of inclusions of titanium nitrides or carbonitrides observed at 1.5 mm from the surface of steels according to the invention and of reference steels, as defined above. The titanium contents of the various steels have also been reported.
  • the maximum size of inclusions of nitrides or carbonitrides of titanium is determined as follows. On a section of rod or wire rod from a given steel casting, a 100mm 2 surface is examined at a location 1.5mm ⁇ 0.5mm below the surface of the bar or wire rod. After these observations, the size of the inclusion of titanium nitride or carbonitride with the largest area is determined by considering that the inclusions are squares and that the size of each of these inclusions, including inclusion having the largest surface, is equal to the square root of this area. All inclusions are observed on a bar or wire rod cut for springs, observations being made on 100mm 2 of this section.
  • the steel casting is in accordance with the invention when the maximum size of the abovementioned inclusions observed over 100 mm 2 at 1.5 mm ⁇ 0.5 mm below the surface is less than 20 ⁇ m.
  • the corresponding results obtained on steels according to the invention and reference steels are given in Table 3.
  • Samples for fatigue tests were taken from bars, the final diameter of specimen samples being 11 mm.
  • the preparation of fatigue test samples includes coarse machining, austenitization, oil quenching, tempering, grinding and shot blasting. These samples were tested for fatigue-torsion in air. The shear stress applied was 856 ⁇ 494 MPa and the number of cycles to failure was counted. The tests were stopped after 2.10 6 cycles if the samples were not broken.
  • Moisture resistance was determined using a cyclic compression test on cylindrical samples. The diameter of the samples was 7mm and their height 12mm. They were taken from the steel bars.
  • the manufacture of the specimens of chill tests included rough machining, austenitization, oil quenching, tempering and final fine grinding.
  • the height of the sample was measured precisely before the start of the test using a comparator with a precision of 1 ⁇ m.
  • a preload was applied to simulate the pretensioning of the springs, this pretensioning being a compressive stress of 2200MPa.
  • the reference steel 1 has, in particular, a sulfur content too high to achieve a good compromise between the fatigue resistance in the air and the fatigue content under corrosion.
  • its manganese content is too high, resulting segregations damaging to the homogeneity of the steel and fatigue resistance in the air.
  • Reference steel 2 has a carbon content and a carbon equivalent that is too low to ensure high hardness. Its tensile strength is too low for good resistance to fatigue in the air.
  • the reference steel 3 has, in particular, a silicon content that is too low to ensure good resistance to scumming, and also good resistance to fatigue in the air.
  • the wear resistance is higher for the steels of the invention than for the reference steels, as shown in FIG. figure 1 , where it is clear that, according to the aforementioned abatement measures, the abatement values are at least 32% lower for the worst case of the steels of the invention (steel of the invention 1) compared to the best case of reference steels (reference steel 1).
  • the fatigue life in the air is significantly higher for the steels of the invention compared to the reference steels. This is due to the increase in hardness, as shown by the figure 2 . But an increase in hardness is not enough.
  • steels of high hardness are all the more sensitive to defects, such as inclusions and surface defects, the hardness is higher.
  • the steels according to the invention are less sensitive to defects, in particular to large inclusions such as titanium nitrides or carbonitrides, in view of the fact that the invention avoids the appearance of such oversized inclusions.
  • Table 3 the largest inclusions found in the steels according to the invention do not exceed the size of 14.1 ⁇ m, whereas inclusions larger than 20 ⁇ m are in the reference steel 2.
  • the slightest sensitivity to surface defects such as those that may occur during the manufacture of the spring or other operations when using steels of the invention can be illustrated by resilience tests performed on the steels of the invention and reference steels which have been heat-treated and have hardnesses of 55HRC or more, see figure 3 .
  • the values measured during Charpy resilience tests on the steels of the invention (where the notch of the specimen simulates a concentration of stresses like other stress concentrations that may be encountered on surface defects produced during spring manufacture or other operations) are higher than those measured on the reference steels. This shows that the steels according to the invention are less sensitive to the concentrations of stress on the defects than the reference steels according to the prior art.
  • the steels according to the invention have the advantage that their resistance to fatigue under corrosion is higher than that of the reference steels according to the prior art, and in particular for hardnesses greater than 55HRC such as. show it figure 4 .
  • the invention makes it possible to obtain a higher hardness with a good compromise between the fatigue life in the air and a resistance to weariness that are greatly increased, and a fatigue life under corrosion which is better than that of the reference steel according to the prior art.

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Claims (5)

  1. Federstahl mit verbessertem Ermüdungsverhalten in Luft und bei Korrosion und mit hoher Widerstandsfähigkeit gegen zyklisches Erschlaffen mit einer Zusammensetzung in Gewichtsprozenten:
    C = 0,45 - 0,70 %
    Si = 1,65 - 2, 50 %
    Mn = 0,20 - 0,75 %
    Cr = 0,60 - 2 %
    Ni = 0,15 - 1 %
    Mo = Spuren - 1 %
    V = 0,003 - 0,8 %
    Cu = 0,10 - 1 %
    Ti = 0,020 - 0,2 %
    Nb = Spuren - 0,2 %
    Al = 0,002 - 0,050 %
    P = Spuren - 0,015 %
    S = Spuren - 0,015 %
    O = Spuren - 0,0020 %
    N = 0,0020 - 0,0110 %,
    wobei der Rest Eisen und aus der Herstellung resultierende Verunreinigungen ist und wobei dessen Gehalt an gleichwertigen Kohlenstoff Ceq, berechnet nach der Formel Ceq % = C % + 0 , 12 Si % + 0 , 17 Mn % - 0 , 1 Ni % + 0 , 13 Cr % - 0 , 24 V %
    Figure imgb0005
    zwischen 0,80 und 1,00 % liegt und dessen Härte nach Abschrecken und Vergüten größer oder gleich 55 HRC ist,
    wobei die maximale Größe der Nitride oder Carbonnitride des TI, beobachtet bei 1,5 ± 0,5 mm der Fläche einer Stange oder eines Walzdrahtes, einer Luppe oder einer Feder auf 100 mm2 der Schnittoberfläche kleiner oder gleich 20 µm ist, wobei die Größe gleich der Quadratwurzel der Fläche der als Quadrate angesehenen Einschlüsse ist.
  2. Federstahl nach Anspruch 1, dadurch gekennzeichnet, dass seine Zusammensetzung ist:
    C = 0,45 - 0,65 %
    Si = 1,65 - 2,20 %
    Mn = 0,20 - 0,65 %
    Cr = 0,80 - 1,7 %
    Ni = 0,15 - 0,80 %
    Mo = Spuren - 0,80 %
    V = 0,003 - 0,5 %
    Cu = 0,10 - 0,90 %
    Ti = 0,020 - 0,15 %
    Nb = Spuren - 0,15 %
    Al = 0,002 - 0,050 %
    P = Spuren - 0,010 %
    S = Spuren - 0,010 %
    O = Spuren - 0,0020 %
    N = 0,0020 - 0,0110 %,
    wobei der Rest Eisen und aus der Herstellung resultierende Verunreinigungen ist.
  3. Verfahren zur Herstellung eines Federstahls mit verbessertem Ermüdungsverhalten bei Luft und bei Korrosion und mit hoher Widerstandsfähigkeit gegen zyklisches Erschlaffen, nach dem man in einem Konverter oder einem-elektrischen Ofen einen flüssigen Stahl herstellt, man seine Zusammensetzung einstellt, man ihn in Form von Vorblöcken oder Barren von kontinuierlichem Guss oder Blöcken gießt, die man bei Umgebungsluft erkalten lässt, man ihn in Form von Barren, Walzdraht oder Luppen auswalzt und man ihn in Federn umformt, dadurch gekennzeichnet, dass:
    - der Stahl von dem Typ nach einem der Ansprüche 1 oder 2 ist;
    - man auf die Vorblöcke, die Barren oder Blöcke während oder nach ihrer Verfestigung eine mittlere minimale Abkühlgeschwindigkeit von 0,3°C/s zwischen 1450 und 1300°C aufbringt;
    - man die Vorblöcke, Barren oder Blöcke zwischen 1200 und 800°C in ein oder zwei Zyklen der Vorwärmung und des Walzens auswalzt;
    - und man auf die Barren, die Walzdrähte oder die Luppen oder auf die Federn, die daraus herrühren, eine Austenitisierung zwischen 850 und 1000°C, gefolgt von einem Abschrecken in Wasser, einem Polymerabschrecken oder einem Ölabschrecken und von einem Vergüten bei 300-550°C aufbringt, derart, dass dem Stahl eine erhöhte Härte oder Härte gleich 55 HRC mitgeteilt wird.
  4. Feder, dadurch gekennzeichnet, dass sie aus Stahl nach einem der Ansprüche 1 bis 2 ist.
  5. Feder nach Anspruch 4, dadurch gekennzeichnet, dass sie aus einem Stahl ist, der durch das Verfahren nach dem Anspruch 3 erhalten wird.
EP06841905A 2005-12-15 2006-12-11 Federstahl, verfahren zur herstellung einer feder aus diesem stahl und eine feder aus diesem stahl Active EP1966407B1 (de)

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