EP1905857A2 - High-strength steel and applications for such steel - Google Patents
High-strength steel and applications for such steel Download PDFInfo
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- EP1905857A2 EP1905857A2 EP07116927A EP07116927A EP1905857A2 EP 1905857 A2 EP1905857 A2 EP 1905857A2 EP 07116927 A EP07116927 A EP 07116927A EP 07116927 A EP07116927 A EP 07116927A EP 1905857 A2 EP1905857 A2 EP 1905857A2
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 119
- 239000010959 steel Substances 0.000 title claims abstract description 119
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 3
- 229910000734 martensite Inorganic materials 0.000 claims description 31
- 238000004519 manufacturing process Methods 0.000 claims description 13
- 229910000859 α-Fe Inorganic materials 0.000 claims description 6
- 238000002347 injection Methods 0.000 claims description 2
- 239000007924 injection Substances 0.000 claims description 2
- 238000011089 mechanical engineering Methods 0.000 claims description 2
- 238000005065 mining Methods 0.000 claims description 2
- 230000003534 oscillatory effect Effects 0.000 claims description 2
- 230000002787 reinforcement Effects 0.000 claims description 2
- 239000003381 stabilizer Substances 0.000 claims description 2
- 239000010955 niobium Substances 0.000 abstract description 18
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract description 14
- 239000010936 titanium Substances 0.000 abstract description 13
- 239000011572 manganese Substances 0.000 abstract description 11
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 10
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 abstract description 4
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 abstract description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 abstract description 3
- 239000011733 molybdenum Substances 0.000 abstract description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 abstract 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 abstract 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 abstract 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 abstract 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 abstract 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 abstract 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract 1
- 239000011651 chromium Substances 0.000 abstract 1
- 239000011574 phosphorus Substances 0.000 abstract 1
- 239000010703 silicon Substances 0.000 abstract 1
- 239000011593 sulfur Substances 0.000 abstract 1
- 238000001816 cooling Methods 0.000 description 26
- 230000000694 effects Effects 0.000 description 11
- 229910001563 bainite Inorganic materials 0.000 description 10
- 238000005275 alloying Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 7
- 238000005496 tempering Methods 0.000 description 6
- 238000006243 chemical reaction Methods 0.000 description 4
- 230000035945 sensitivity Effects 0.000 description 4
- 238000011282 treatment Methods 0.000 description 4
- 239000002131 composite material Substances 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000011265 semifinished product Substances 0.000 description 2
- 238000001228 spectrum Methods 0.000 description 2
- -1 titanium nitrides Chemical class 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- VCTOKJRTAUILIH-UHFFFAOYSA-N manganese(2+);sulfide Chemical class [S-2].[Mn+2] VCTOKJRTAUILIH-UHFFFAOYSA-N 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 150000002822 niobium compounds Chemical class 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 210000002023 somite Anatomy 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Images
Classifications
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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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/001—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
- C22C38/02—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
- C22C38/06—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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/26—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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
Definitions
- the invention relates to a steel having a high tensile strength and uses of such a steel.
- AFP steels which are standardized in DIN EN 10267 and have a ferrite / pearlitic structure, do not achieve the combination of high strength and fracture deformation characteristics required here.
- a common disadvantage of the known high-strength materials is moreover that they only reach the respective strength level after an additional tempering treatment.
- a steel with good deformation properties, but at the same time also with sufficient strength is to be from the EP 1 264 910 A1 known.
- the known steel contains (in% by weight) in addition to iron and unavoidable impurities as essential components 0.0005 - 0.30% C, 0.001 - 2.0% Si and 0.01 - 3.0% Mn.
- the known steel may contain a variety of other optional alloying elements to emphasize certain properties of this steel.
- the known steel can also optionally contain Nb, Ti and V contents with a sum of the contents of these elements of 0.001-0.5% by weight and 0.001-0.20% by weight of P and 0.0001. 0.03 wt .-% N are added.
- the known steel may contain, in total, 0.001 - ⁇ 1.5% by weight Cr, Mo, Ni, Co and / or W.
- the Cr contents were regularly at 0.2 wt .-%, while the contents of Nb regularly 0.02 wt .-% were.
- the Cr content of the known steel should preferably be below 0.6%. Accordingly, included in the EP 0 974 678 B1 Illustrated embodiments each Cr contents in the range of less than 0.3%. In addition, none of these embodiments, effective levels of Nb, Ti or N, since these elements according to the in the EP 0 974 678 B1 summarized findings, the hardness in the area of the welds undesirably high.
- a steel according to the invention is composed by a suitable choice of the alloying elements that it converts after cooling in air from the hot rolling heat or forging heat in a fine-grained, tough, martensitic structure and in this way without additional heat treatment high tensile strength values of more than 1100 N. / mm 2 reached.
- the structure of the steel according to the invention can be determined by choosing a suitable cooling rate between a substantially pure martensitic or martensitic, Shares of lower bainite comprehensive and a ferritic-bainitic-martensitic structure can be varied.
- a cooling rate of more than 0.5 K / s between 800 and 500 ° C reliably establishes a completely martensitic microstructure or a structure with martensite and lower bainite, while at lower cooling rates the bainite content in the microstructure increases and only at slower cooling rates of less than 0.2 K / s ferrite in the structure occur.
- thermomechanical hot forming rolling or forging
- a subsequent controlled cooling in the temperature range between 800 and 500 ° C with a cooling rate of approx. 0.05 K / s produce a duplex structure consisting of 15-30% ferrite and 70-85% martensite (including lower bainite).
- the hot-formed semifinished product can be cooled from forming temperatures between 950 and 1100 ° C. to a cross-sectional equivalent of 2830 mm 2 in air.
- the C content of a steel according to the invention is at least 0.15% by weight in order to ensure the weldability and the ductility of the set hardening structure. In this way, a good combination of high strength and ductility is achieved without a subsequent tempering of the structure.
- the C content is limited to a maximum of 0.3 wt% in order to avoid the formation of hot cracks after welding and excessive distortion of the tetragonal texture of the martensite. The latter leads to a reduction in the ductility properties in the unannealed state.
- the Si content of a steel according to the invention is in the range of 0.1-0.5% by weight in order to avoid additional solidification of the steel matrix and thus to keep the ductility degradation in the unannealed state low.
- Mn is present in a steel according to the invention in amounts of at least 0.6% by weight in order to achieve sufficient hardenability of the steel with the aid of this inexpensive alloying element. More than 1.8% by weight should not be present in steel according to the invention, otherwise excessive segregation of this alloying element may occur, which would impair the combination of strength and ductility.
- the effect of Mn used according to the invention in steel according to the invention is optimal when the Mn content is 1.6-1.8% by weight.
- the presence of Cr in contents of 1.0-1.8% by weight is of particular importance for the steel alloyed according to the invention.
- Cr an increase in the hardenability of the steel is achieved without substantially changing the temperature of conversion to the martensite stage (also called the martensite start temperature "Ms").
- Ms martensite start temperature
- a self-tempering effect of the hardening structure due to the cooling from the hot working temperatures is achieved, which gives the steel according to the invention a good combination of high strength and ductility after cooling from hot working temperatures without further tempering treatment.
- This effect can be achieved particularly reliably if the Cr content is 1.5-1.8% by weight, in particular 1.5-1.7% by weight.
- Mo is present in a steel of the present invention at levels of 0.10-0.50 weight percent to extend the conversion range in the martensite and lower bainite levels. With this measure, it is possible to set larger semifinished product dimensions with the desired microstructure constituents which determine the strength and ductility characteristic values obtained according to the invention. At contents of less than 0.1% by weight, this effect does not occur to the desired extent, while contents of more than 0.5% by weight lead to no significant improvement in the properties, but merely unnecessarily increase the cost of the steel according to the invention.
- the effect of molybdenum used according to the invention is particularly safe if the Mo content is in the range from 0.2 to 0.4% by weight.
- Steel according to the invention may contain up to 0.50% by weight of nickel to promote the ductility of the steel matrix. At higher levels of Ni, no significant improvements of the steel according to the invention occur for the property profile required according to the invention. Therefore, the Ni content of steel according to the invention should preferably be at most 0.2 wt .-%.
- Ti is present in grades of 0.020-0.060 wt% of steel in accordance with the present invention to assure fine granularity at elevated temperatures. This effect is achieved particularly reliably when the Ti content of the steel according to the invention is 0.025-0.045% by weight.
- Al is added to steel in accordance with the invention for purposes of deoxidation at levels of 0.010-0.060 wt%.
- N is added to steels of the present invention at levels of 0.008-0.030 weight percent to facilitate the formation of niobium and titanium nitrides.
- the precipitates of niobium and titanium nitrides are very effective for grain refinement.
- P content is set to less than 0.030 wt .-%. At higher P contents is to be expected with a deterioration of the ductility properties.
- Steel composed according to the invention has a fine-grained, tough martensitic structure after hot rolling or hot forging followed by cooling in still air. This applies in particular if the alloying ranges for Mn, Cr, Mo, Nb, Ti and Ni, which are each referred to as particularly favorable, are adhered to.
- Steel according to the invention because of its fine-grained, tough martensite-containing structure, is suitable for pressure-tight components for diesel injection systems which are stressed at pressures of up to 3,000 bar.
- the low medium-voltage sensitivity of steel according to the invention also makes steel according to the invention also for the production of components particularly suitable, which are subjected to oscillating in the train-Schwell- and in the train-pressure area. Components of this type are needed in particular in the automotive industry or generally in the field of the construction of internal combustion engines.
- steels according to the invention are furthermore particularly suitable for the production of high-strength components, such as sling chains, chain locks, mining chains and chains for securing motorcycles and bicycles, or for the production of fastening elements. like nuts and bolts.
- components can be produced which are surface-treated.
- the surface treatment can be carried out as case hardening, nitriding, nitrocarburizing or as laser beam treatment.
- the correspondingly treated articles may in particular be wear-resistant, pressure-tight components which are used under oscillating stress even at operating temperatures of up to 450.degree.
- Another use according to the invention of a steel according to the invention consists in flat products which are punched and deposited in air.
- a flat product may, for example, be the B-pillar of an automobile body.
- steel according to the invention is particularly suitable for the production of hot-formed and air-laid tubes and flat bars, which are used, for example, as reinforcement of doors against side impact in passenger and commercial vehicles.
- steels according to the invention can be used particularly well in general form for the production of hot or cold formed, high strength and generally used in mechanical engineering components.
- Cold piled tubes or cold rolled flat bars with increased strength can be produced just as well from steels according to the invention.
- Table 1 shows by way of example a composition of a steel according to the invention. This steel has been smelted, cast into a billet in the strand and hot rolled into bars and wire. Subsequently, various samples of this steel have been cooled at different rates.
- the steel according to the invention thus converts from the austenitizing temperature into the martensite stage by suitable cooling and achieves an unexpectedly good combination of strength and fracture deformation characteristics (ductility) because of the fine graininess of the microstructure and the self-tempering effect during the cooling process.
- ductility strength and fracture deformation characteristics
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- Heat Treatment Of Steel (AREA)
Abstract
Description
Die Erfindung betrifft einen Stahl mit einer hohen Zugfestigkeit und Verwendungen eines solchen Stahls.The invention relates to a steel having a high tensile strength and uses of such a steel.
Seitens der Industrie werden für immer höhere mechanische Beanspruchungen von Bauteilen für Maschinen und Motoren kostengünstige Werkstoffe gesucht, die ausgehend von hohen Mittelspannungen steigenden Dauerbelastungen im Zug-Schwell-Bereich ausgesetzt sind. Je höher die Mittelspannung ist, von der die Zug-Schwell-Beanspruchung angelegt wird, desto größer ist die Empfindlichkeit hochfester Stähle gegenüber einer Dauerbeanspruchung. Gerade für Bauteile, die bei hohen Drücken von über 2000 bar beansprucht werden, kommt der Mittelspannungsempfindlichkeit eines Werkstoffes eine große Bedeutung zu. Zudem werden den Werkstoffen eine gute Schweißeignung und eine ausreichende spanabhebende Bearbeitbarkeit abverlangt.The industry is looking for higher and higher mechanical stresses of components for machines and motors cost-effective materials, which are exposed starting from high medium voltages increasing continuous loads in the train-Schwell range. The higher the center stress of which the tensile-to-threshold stress is applied, the greater the sensitivity of high-strength steels to continuous stress. Especially for components that are stressed at high pressures of over 2000 bar, the medium-voltage sensitivity of a material is of great importance. In addition, the materials are required to have good weldability and sufficient machinability.
Aus dem Stand der Technik ist eine ganze Reihe von hochfesten Stählen bekannt. Dazu zählen die in der DIN EN 10084, 10269 oder 10083 genormten Stähle (z. B. die Stähle 30CrNiM08 (1.6580); 34CrNiM06 (1.6582), 36CrNiM04 (1.6511), 18CrNiMo 7-6 (1.6587), 17CrNi6-6 (1.5918), 14NiCrMo13-4 (1.6657)) oder die Stähle 31CrMoV9 (1.8519), 33CrMoVI2-9(1.8522) oder 21CrMoV5-7 (1.7709), die unter die DIN EN 10085 fallen. Allerdings sind diese bekannten hochfesten Stähle jeweils mit Nickel, Molybdän bzw. Vanadium legiert.From the prior art, a whole series of high-strength steels is known. These include the steels standardized in DIN EN 10084, 10269 or 10083 (eg the steels 30CrNiM08 (1.6580), 34CrNiM06 (1.6582), 36CrNiM04 (1.6511), 18CrNiMo 7-6 (1.6587), 17CrNi6-6 (1.5918) , 14NiCrMo13-4 (1.6657)) or the steels 31CrMoV9 (1.8519), 33CrMoVI2-9 (1.8522) or 21CrMoV5-7 (1.7709), which fall under DIN EN 10085. However, these are known high strength steels each alloyed with nickel, molybdenum or vanadium.
Diese Legierungselemente leiden in letzter Zeit unter stark schwankenden Preisen. Aufgrund dieser Preisvolatilität können die Kosten der Herstellung von Bauteilen, die aus Stählen der voranstehend angegebenen Art hergestellt sind, nicht mit der für eine vernünftige kaufmännische Planung notwendigen Sicherheit abgeschätzt werden. Im Ergebnis erweist sich daher die Erzeugung von Bauteilen aus den bekannten Stählen vielfach als unwirtschaftlich.These alloying elements have been suffering from fluctuating prices lately. Due to this price volatility, the cost of manufacturing components made from steels of the above stated type can not be estimated with the safety required for sound business planning. As a result, therefore, the production of components from the known steels often proves to be uneconomical.
Andere Werkstoffe, wie die in der DIN EN 10084 oder 10089 genormten Stähle 51CrV4 (1.8159), 50 CrM04 (1.7228), 42CrM04 (1.7225) oder 46SiCrM06 (1.8062), enthalten zwar hinsichtlich ihrer Preisentwicklung weniger kritische Legierungselemente, besitzen jedoch eine für die hier interessierenden Anwendungen nur unzulängliche Schweißbarkeit.Other materials, such as the steels 51CrV4 (1.8159), 50 CrM04 (1.7228), 42CrM04 (1.7225) or 46SiCrM06 (1.8062) standardized in DIN EN 10084 or 10089, contain less critical alloying elements in terms of their price development, but have one for the here applications of interest only inadequate weldability.
Andere Stähle, wie die in der DIN EN 10267 genormten, ein Ferrit-/Perlit-Gefüge aufweisenden so genannten "AFP-Stähle", erreichen die hier geforderte Kombination aus hoher Festigkeit und Bruchverformungskennwerten nicht.Other steels, such as the so-called "AFP steels", which are standardized in DIN EN 10267 and have a ferrite / pearlitic structure, do not achieve the combination of high strength and fracture deformation characteristics required here.
Ein gemeinsamer Nachteil der bekannten hochfesten Werkstoffe besteht darüber hinaus darin, dass sie nur nach einer zusätzlichen Vergütungsbehandlung das jeweilige Festigkeitsniveau erreichen.A common disadvantage of the known high-strength materials is moreover that they only reach the respective strength level after an additional tempering treatment.
Ein Stahl mit guten Verformungseigenschaften, der jedoch gleichzeitig auch über eine ausreichende Festigkeit verfügen soll, ist aus der
Aus der
Schließlich ist aus der
Vor dem Hintergrund des voranstehend erläuterten Standes der Technik lag der Erfindung die Aufgabe zu Grunde, einen Stahl zu entwickeln, der unter Verwendung von kostengünstig erhältlichen Legierungszusätzen und ohne nachträgliche Vergütungsbehandlung über 1100 N/mm2 liegende Zugfestigkeitswerte erreicht. Darüber hinaus sollten vorteilhafte Verwendungen eines solchen Stahls angegeben werden.Against the background of the prior art described above, the object of the invention was to develop a steel which achieves tensile strength values above 1100 N / mm 2 using alloy additives which are available at low cost and without subsequent tempering treatment. In addition, advantageous uses of such a steel should be indicated.
In Bezug auf den Werkstoff ist diese Aufgabe erfindungsgemäß durch den in Anspruch 1 angegebenen Stahl gelöst worden. Vorteilhafte Ausgestaltungen dieses Stahls sind in den auf Anspruch 1 rückbezogenen Ansprüchen angegeben.With regard to the material, this object has been achieved according to the invention by the steel specified in claim 1. Advantageous embodiments of this steel are given in the claims back to claim 1.
Vorteilhafte, die oben genannte Aufgabe ebenfalls lösende Verwendungen des erfindungsgemäßen Stahls sind beginnend mit Anspruch 12 genannt.Advantageous, the above object also solving uses of the steel according to the invention are beginning with claim 12 called.
Ein erfindungsgemäßer Stahl ist durch eine geeignete Wahl der Legierungselemente so zusammengesetzt, dass er nach dem Abkühlen an Luft aus der Warmwalzhitze oder aus der Schmiedehitze in ein feinkörniges, zähes, martensitisches Gefüge umwandelt und auf diesem Wege ohne zusätzliche Wärmebehandlung hohe Zugfestigkeitswerte von mehr als 1100 N/mm2 erreicht.A steel according to the invention is composed by a suitable choice of the alloying elements that it converts after cooling in air from the hot rolling heat or forging heat in a fine-grained, tough, martensitic structure and in this way without additional heat treatment high tensile strength values of more than 1100 N. / mm 2 reached.
Zu beachten ist, dass die Unterscheidung der Härtungsgefügeanteile zwischen "Martensit" und "unterem Bainit" in einem feinkörnigen Gefüge unter einem Mikroskop in der Praxis oft schwierig ist. Daher kann häufig nicht ausgeschlossen werden, dass je nach Geschwindigkeit der Abkühlung aus der Warmumformhitze im Gefüge der erhaltenen Stäbe oder des erhaltenen Walzdrahts neben Martensit auch Anteile von unterem Bainit vorliegen, ohne dass dies ohne weiteres erkennbar ist. Sofern dies nicht ausdrücklich ausgeschlossen ist, sind daher nach Verständnis der vorliegenden Erfindung von den jeweils erwähnten Martensit-Gefügeanteilen eines erfindungsgemäßen Stahls immer auch eventuell neben dem Martensit-Anteil zusätzlich vorhandene Anteile an unterem Bainit umfasst, ohne dass es dazu einer ausdrücklichen Erwähnung bedarf.It should be noted that the distinction between the hardened microstructure proportions between "martensite" and "lower Bainite "in a fine-grained microstructure under a microscope is often difficult in practice, therefore it can often not be excluded that, depending on the rate of cooling from the hot-forming heat in the microstructure of the rods obtained or the wire rod obtained, in addition to martensite also lower bainite fractions, Unless this is expressly excluded, it is understood that the above-mentioned martensite constituents of a steel according to the invention always include, in addition to the martensite fraction, additionally present fractions of lower bainite, without understanding it needs an explicit mention.
Praktische Untersuchungen haben ergeben, dass im Rahmen der erfindungsgemäßen Legierungsvorschrift zusammengesetzte Stähle regelmäßig Zugfestigkeiten erreichen, die mindestens 1200 N/mm2 betragen, insbesondere bei über 1250 N/mm2 liegen. Gleichzeitig weisen die erfindungsgemäß beschaffenen Stähle hohe Bruchverformungskennwerte auf, die unter anderem durch eine mehr als 30 %, insbesondere mehr als 35 %, betragende, eine hohe Duktilität kennzeichnende Brucheinschnürung gekennzeichnet sind. Gleichzeitig weisen erfindungsgemäß zusammengesetzte Stähle unter schwingender Beanspruchung eine hohe Dauerwechselfestigkeit im Zug-Schwell-Bereich mit einer geringen Mittelspannungsempfindlichkeit auf.Practical investigations have shown that in the alloy rule according to the invention composite steels regularly reach tensile strengths which amount to at least 1200 N / mm 2 , in particular at more than 1250 N / mm 2 . At the same time, the steels obtained according to the invention have high fracture deformation characteristics, which are characterized inter alia by a fracture constriction which is more than 30%, in particular more than 35%, and characterizes a high ductility. At the same time, steels composed according to the invention have a high fatigue strength in the tensile-threshold region with a low medium-voltage sensitivity under oscillatory stress.
Das Gefüge des erfindungsgemäßen Stahls kann durch Wahl einer geeigneten Abkühlgeschwindigkeit zwischen einem im Wesentlichen rein martensitischen bzw. martensitischen, Anteile von unterem Bainit umfassenden und einem ferritisch-bainitisch-martensitischen Gefüge variiert werden. So stellt sich bei über 0,5 K/s liegenden Abkühlraten zwischen 800 und 500 °C zuverlässig ein vollständig martensitisches Gefüge oder ein Gefüge mit Martensit und unterem Bainit ein, während bei darunter liegenden Abkühlraten der Bainit-Anteil im Gefüge zunimmt und erst bei noch langsameren Abkühlungsgeschwindigkeiten von unter 0,2 K/s Ferritanteile im Gefüge auftreten.The structure of the steel according to the invention can be determined by choosing a suitable cooling rate between a substantially pure martensitic or martensitic, Shares of lower bainite comprehensive and a ferritic-bainitic-martensitic structure can be varied. For example, a cooling rate of more than 0.5 K / s between 800 and 500 ° C reliably establishes a completely martensitic microstructure or a structure with martensite and lower bainite, while at lower cooling rates the bainite content in the microstructure increases and only at slower cooling rates of less than 0.2 K / s ferrite in the structure occur.
Dem folgend lässt sich beispielsweise durch ein thermomechanisches Warmumformen (Walzen oder Schmieden) des erfindungsgemäßen Stahls zu Draht oder Stabstahl und einer anschließenden kontrollierten Abkühlung im Temperaturbereich zwischen 800 und 500 °C mit einer Abkühlungsgeschwindigkeit von rd. 0,05 K/s ein Duplex-Gefüge erzeugen, das zu 15 - 30 % aus Ferrit und zu 70 - 85 % aus Martensit (einschl. unterem Bainit) besteht.The following can be, for example, by a thermomechanical hot forming (rolling or forging) of the steel according to the invention into wire or steel bar and a subsequent controlled cooling in the temperature range between 800 and 500 ° C with a cooling rate of approx. 0.05 K / s produce a duplex structure consisting of 15-30% ferrite and 70-85% martensite (including lower bainite).
Soll dagegen ein im Wesentlichen martensitisches Gefüge mit Anteilen von unterem Bainit erhalten werden, so kann dazu das warmumgeformte Halbzeug von Umformtemperaturen zwischen 950 und 1100 °C bis zu einem Querschnittsäquivalent von 2830 mm2 an Luft abgekühlt werden.If, on the other hand, a substantially martensitic structure with proportions of lower bainite is to be obtained, then the hot-formed semifinished product can be cooled from forming temperatures between 950 and 1100 ° C. to a cross-sectional equivalent of 2830 mm 2 in air.
Der C-Gehalt eines erfindungsgemäßen Stahls beträgt mindestens 0,15 Gew.-%, um die Schweißbarkeit und die Duktilität des eingestellten Härtungsgefüges sicherzustellen. Auf diese Weise wird auch ohne ein nachträgliches Anlassen des Gefüges eine gute Kombination von hoher Festigkeit und Duktilität erreicht.The C content of a steel according to the invention is at least 0.15% by weight in order to ensure the weldability and the ductility of the set hardening structure. In this way, a good combination of high strength and ductility is achieved without a subsequent tempering of the structure.
Gleichzeitig ist der C-Gehalt auf maximal 0,3 Gew.-% beschränkt, um die Bildung von Heißrissen nach dem Schweißen und eine übermäßige Verzerrung der tetragonalen Gefügestruktur des Martensits zu vermeiden. Letzteres führt zu einer Verringerung der Duktilitätseigenschaften im nicht angelassenen Zustand.At the same time, the C content is limited to a maximum of 0.3 wt% in order to avoid the formation of hot cracks after welding and excessive distortion of the tetragonal texture of the martensite. The latter leads to a reduction in the ductility properties in the unannealed state.
Der Si-Gehalt eines erfindungsgemäßen Stahls liegt im Bereich von 0,1 - 0,5 Gew.-%, um eine zusätzliche Verfestigung der Stahlmatrix zu vermeiden und somit den Duktilitätsabbau im nicht angelassenen Zustand gering zu halten.The Si content of a steel according to the invention is in the range of 0.1-0.5% by weight in order to avoid additional solidification of the steel matrix and thus to keep the ductility degradation in the unannealed state low.
Mn ist in einem erfindungsgemäßen Stahl in Gehalten von mindestens 0,6 Gew.-% vorhanden, um eine ausreichende Härtbarkeit des Stahles mit Hilfe dieses preiswerten Legierungselements zu erreichen. Mehr als 1,8 Gew.-% sollen in erfindungsgemäßem Stahl nicht vorhanden sein, da andernfalls eine übermäßige Seigerung dieses Legierungselementes eintreten kann, welche die Kombination von Festigkeit und Duktilität beeinträchtigen würde. Optimal ist die erfindungsgemäß genutzte Wirkung von Mn in erfindungsgemäßem Stahl, wenn der Mn-Gehalt 1,6 - 1,8 Gew.-% beträgt.Mn is present in a steel according to the invention in amounts of at least 0.6% by weight in order to achieve sufficient hardenability of the steel with the aid of this inexpensive alloying element. More than 1.8% by weight should not be present in steel according to the invention, otherwise excessive segregation of this alloying element may occur, which would impair the combination of strength and ductility. The effect of Mn used according to the invention in steel according to the invention is optimal when the Mn content is 1.6-1.8% by weight.
Der Anwesenheit von Cr in Gehalten von 1,0 - 1,8 Gew.-% kommt beim erfindungsgemäß legierten Stahl eine besondere Bedeutung zu. Durch Cr wird eine Erhöhung der Härtbarkeit des Stahles erreicht, ohne die Temperatur der Umwandlung in die Martensitstufe (auch die Martensit-StartTemperatur "Ms" genannt) wesentlich zu verändern. Damit wird ein Selbstanlasseffekt des Härtungsgefüges infolge der Abkühlung von den Warmumformtemperaturen erzielt, was dem erfindungsgemäßen Stahl eine gute Kombination von hoher Festigkeit und Duktilität nach dem Abkühlen von den Warmumformtemperaturen ohne eine weitere Anlassbehandlung verleiht. Besonders sicher lässt sich diese Wirkung dann erzielen, wenn der Cr-Gehalt 1,5 - 1,8 Gew.-%, insbesondere 1,5 - 1,7 Gew.-%, beträgt.The presence of Cr in contents of 1.0-1.8% by weight is of particular importance for the steel alloyed according to the invention. By Cr, an increase in the hardenability of the steel is achieved without substantially changing the temperature of conversion to the martensite stage (also called the martensite start temperature "Ms"). Thus, a self-tempering effect of the hardening structure due to the cooling from the hot working temperatures is achieved, which gives the steel according to the invention a good combination of high strength and ductility after cooling from hot working temperatures without further tempering treatment. This effect can be achieved particularly reliably if the Cr content is 1.5-1.8% by weight, in particular 1.5-1.7% by weight.
Mo ist in einem erfindungsgemäßen Stahl in Gehalten von 0,10 - 0,50 Gew.-% vorhanden, um den Umwandlungsbereich in der Martensit- und der unteren Bainitstufe zu erweitern. Mit dieser Maßnahme lassen sich größere Halbzeugabmessungen mit den gewünschten Gefügebestandteilen einstellen, die die erfindungsgemäß erzielten Festigkeits- und Duktilitätskennwerte bedingen. Bei Gehalten von weniger als 0,1 Gew.-% tritt diese Wirkung nicht in dem gewünschten Maß ein, während Gehalte von über 0,5 Gew.-% zu keiner wesentlichen Verbesserung der Eigenschaften führen, sondern den erfindungsgemäßen Stahl lediglich unnötig verteuern würden. Besonders sicher tritt die erfindungsgemäß genutzte Wirkung von Molybdän ein, wenn der Mo-Gehalt im Bereich von 0,2 - 0,4 Gew.-% liegt.Mo is present in a steel of the present invention at levels of 0.10-0.50 weight percent to extend the conversion range in the martensite and lower bainite levels. With this measure, it is possible to set larger semifinished product dimensions with the desired microstructure constituents which determine the strength and ductility characteristic values obtained according to the invention. At contents of less than 0.1% by weight, this effect does not occur to the desired extent, while contents of more than 0.5% by weight lead to no significant improvement in the properties, but merely unnecessarily increase the cost of the steel according to the invention. The effect of molybdenum used according to the invention is particularly safe if the Mo content is in the range from 0.2 to 0.4% by weight.
Erfindungsgemäßer Stahl kann bis zu 0,50 Gew.-% Nickel enthalten, um die Duktilität der Stahlmatrix zu fördern. Bei höheren Gehalten an Ni treten keine für das erfindungsgemäß geforderte Eigenschaftsprofil wesentlichen Verbesserungen des erfindungsgemäßen Stahls auf. Deshalb soll der Ni-Gehalt von erfindungsgemäßem Stahl bevorzugt maximal 0,2 Gew.-% betragen.Steel according to the invention may contain up to 0.50% by weight of nickel to promote the ductility of the steel matrix. At higher levels of Ni, no significant improvements of the steel according to the invention occur for the property profile required according to the invention. Therefore, the Ni content of steel according to the invention should preferably be at most 0.2 wt .-%.
Der Anwesenheit von Nb in Gehalten von 0,030 - 0,150 Gew.-% kommt ebenfalls eine besondere Bedeutung zu. So wird bei einem Mindestgehalt von 0,030 Gew.-% Nb einerseits eine Verfeinerung des Gefüges erreicht. Andererseits erweitern geringe in der Stahlmatrix gelöste Niobanteile den Umwandlungsbereich der Martensit- / unteren Bainitstufe. Gleichzeitig sollten nicht mehr als 0,150 Gew.-% Nb in erfindungsgemäßem Stahl vorhanden sein, um eine übermäßige Ausscheidung von Niobverbindungen auf den Korngrenzen während des Abkühlens von den Warmumformtemperaturen zu vermeiden. Optimierte Wirkungen von Nb in erfindungsgemäßem Stahl werden dann erreicht, wenn der Nb-Gehalt 0,08 - 0,12 Gew.-% beträgt.The presence of Nb at levels of 0.030 - 0.150 wt .-% is also of particular importance. So At a minimum content of 0.030 wt .-% Nb, on the one hand, a refinement of the microstructure is achieved. On the other hand, small amounts of niobium dissolved in the steel matrix broaden the martensite / lower bainite conversion range. At the same time, no more than 0.150 weight percent Nb should be present in steel of the present invention to avoid excessive precipitation of niobium compounds on the grain boundaries during cooling from hot working temperatures. Optimized effects of Nb in steel according to the invention are achieved when the Nb content is 0.08-0.12% by weight.
Ti ist in erfindungsgemäßem Stahl in Gehalten von 0,020 - 0,060 Gew.-% vorhanden, um bei höheren Temperaturen die Feinkörnigkeit des Gefüges zu sichern. Besonders sicher wird diese Wirkung dann erreicht, wenn der Ti-Gehalt des erfindungsgemäßen Stahls 0,025 - 0,045 Gew.-% beträgt.Ti is present in grades of 0.020-0.060 wt% of steel in accordance with the present invention to assure fine granularity at elevated temperatures. This effect is achieved particularly reliably when the Ti content of the steel according to the invention is 0.025-0.045% by weight.
Al wird erfindungsgemäßem Stahl zum Zwecke der Desoxidation in Gehalten von 0,010 - 0,060 Gew.-% zugegeben.Al is added to steel in accordance with the invention for purposes of deoxidation at levels of 0.010-0.060 wt%.
N wird erfindungsgemäßem Stahl in Gehalten von 0,008 - 0,030 Gew.-% zugegeben, um die Bildung von Niob- und Titannitriden zu ermöglichen. Die Ausscheidungen von Niob- und Titannitriden sind sehr wirksam für die Kornverfeinerung.N is added to steels of the present invention at levels of 0.008-0.030 weight percent to facilitate the formation of niobium and titanium nitrides. The precipitates of niobium and titanium nitrides are very effective for grain refinement.
Der in erfindungsgemäßem Stahl vorhandene P-Gehalt wird auf weniger als 0,030 Gew.-% festgelegt. Bei höheren P-Gehalten ist mit einer Beeinträchtigung der Duktilitätseigenschaften zu rechnen.The present in steel according to the invention P content is set to less than 0.030 wt .-%. At higher P contents is to be expected with a deterioration of the ductility properties.
Bei höheren S-Gehalten könnten die Mangansulfide im erfindungsgemäßen Stahl zu stark gestreckt werden und potentielle Bruchstellen der aus dem erfindungsgemäßen Stahl geformten Bauteile bilden. Diese Gefahr gilt es insbesondere dann zu vermeiden, wenn aus erfindungsgemäßem Stahl hochfeste druckdichte Bauteile hergestellt werden. Daher ist der S-Gehalt des erfindungsgemäßen Stahles auf maximal 0,030 Gew.-% beschränkt.At higher S-contents, the manganese sulfides in the steel according to the invention could be stretched too much and form potential break points of the components formed from the steel according to the invention. This danger should be avoided in particular if high-strength pressure-tight components are produced from steel according to the invention. Therefore, the S content of the steel according to the invention is limited to a maximum of 0.030 wt .-%.
Erfindungsgemäß zusammengesetzter Stahl weist nach dem Warmwalzen oder Warmschmieden mit anschließendem Abkühlen an ruhender Luft ein feinkörniges zähes martensitisches Gefüge auf. Dies gilt insbesondere dann, wenn die in den auf Anspruch 1 rückbezogenen, jeweils als besonders günstig angesehenen Legierungsbereiche für Mn, Cr, Mo, Nb, Ti und Ni eingehalten werden.Steel composed according to the invention has a fine-grained, tough martensitic structure after hot rolling or hot forging followed by cooling in still air. This applies in particular if the alloying ranges for Mn, Cr, Mo, Nb, Ti and Ni, which are each referred to as particularly favorable, are adhered to.
Erfindungsgemäßer Stahl eignet sich aufgrund seines feinkörnigen, zähen Martensit enthaltenden Gefüges für druckdichte Bauteile für Dieseleinspritzsysteme, die bei Drücken bis zu 3000 bar beansprucht werden.Steel according to the invention, because of its fine-grained, tough martensite-containing structure, is suitable for pressure-tight components for diesel injection systems which are stressed at pressures of up to 3,000 bar.
Des Weiteren lassen sich aus erfindungsgemäßem Stahl Bauteile erzeugen, die einer Randschichthärtung, insbesondere durch Autofrettage, unterzogen werden.Furthermore, it is possible to produce components from steel according to the invention which undergo surface hardening, in particular by autofrettage.
Die niedrige Mittelspannungsempfindlichkeit erfindungsgemäßen Stahls macht erfindungsgemäßen Stahl darüber hinaus auch für die Herstellung von Bauteilen besonders geeignet, die schwingend im Zug-Schwell- und im Zug-Druck-Bereich beansprucht werden. Bauteile dieser Art werden insbesondere im Bereich der Automobilindustrie oder allgemein im Bereich des Baus von Verbrennungsmotoren benötigt.The low medium-voltage sensitivity of steel according to the invention also makes steel according to the invention also for the production of components particularly suitable, which are subjected to oscillating in the train-Schwell- and in the train-pressure area. Components of this type are needed in particular in the automotive industry or generally in the field of the construction of internal combustion engines.
Aufgrund seines besonderen Eigenschaftsspektrums und seiner vergleichbar niedrigen, gut verlässlich abschätzbaren Herstellkosten sind erfindungsgemäße Stähle des Weiteren besonders geeignet für die Herstellung von hochfesten Bauteilen, wie Anschlagketten, Kettenschlösser, Bergbauketten und Ketten zur Sicherstellung von Motor- und Fahrrädern, oder für die Herstellung von Befestigungselementen, wie Schrauben und Muttern.Because of its special property spectrum and its comparatively low, reliably predictable production costs, steels according to the invention are furthermore particularly suitable for the production of high-strength components, such as sling chains, chain locks, mining chains and chains for securing motorcycles and bicycles, or for the production of fastening elements. like nuts and bolts.
Auch lassen sich aus erfindungsgemäßem Stahl bevorzugt kaltumgeformte, hochfeste Automobilbauteile, insbesondere Stabilisatoren oder Bauteile mit federähnlichen Charakteristiken, erzeugen.It is also possible to produce cold-formed, high-strength automotive components, in particular stabilizers or components with spring-like characteristics, from steel according to the invention.
Ebenso können aus erfindungsgemäßem Stahl Bauteile hergestellt werden, die oberflächenbehandelt werden. Die Oberflächenbehandlung kann dabei als Einsatzhärten, Nitrieren, Nitrocarburieren oder als Laserstrahlbehandelung durchgeführt werden. Bei den entsprechend behandelten Gegenständen kann es sich insbesondere um verschleißbeständige, druckdichte Bauteile handeln, die unter schwingender Beanspruchung auch bei Betriebstemperaturen bis 450 °C eingesetzt werden.Likewise, from steel according to the invention components can be produced which are surface-treated. The surface treatment can be carried out as case hardening, nitriding, nitrocarburizing or as laser beam treatment. The correspondingly treated articles may in particular be wear-resistant, pressure-tight components which are used under oscillating stress even at operating temperatures of up to 450.degree.
Eine andere erfindungsgemäße Verwendung eines erfindungsgemäßen Stahls besteht in Flachprodukten, die im Gesenk geschlagen und an Luft abgelegt sind. Bei einem solchen Flachprodukt kann es sich beispielsweise um die B-Säule einer Automobilkarosserie handeln.Another use according to the invention of a steel according to the invention consists in flat products which are punched and deposited in air. Such a flat product may, for example, be the B-pillar of an automobile body.
Ebenso eignet sich erfindungsgemäßer Stahl besonders für die Herstellung von warmumgeformten und an Luft abgelegten Rohren und Flachstäben, die beispielsweise als Verstärkung von Türen gegen den Seitenaufprall in Personen- und Nutzfahrzeugen eingesetzt werden.Likewise, steel according to the invention is particularly suitable for the production of hot-formed and air-laid tubes and flat bars, which are used, for example, as reinforcement of doors against side impact in passenger and commercial vehicles.
Auch lassen sich erfindungsgemäße Stähle besonders gut in allgemeiner Form zur Herstellung von warm- oder kaltumgeformten, hochfesten und im allgemeinen Maschinenbau eingesetzten Bauteilen verwenden.Also steels according to the invention can be used particularly well in general form for the production of hot or cold formed, high strength and generally used in mechanical engineering components.
Kaltgepilgerte Rohre oder kaltgewalzte Flachstäbe mit erhöhter Festigkeit lassen sich ebenso gut aus erfindungsgemäßen Stählen erzeugen. Dasselbe gilt für die Herstellung von Pistolen- und Gewehrläufen sowie Pistolen- und Gewehrverschlüssen aus erfindungsgemäßen Stählen.Cold piled tubes or cold rolled flat bars with increased strength can be produced just as well from steels according to the invention. The same applies to the production of pistol and rifle barrels as well as pistol and gun closures from steels according to the invention.
Nachfolgend wird die Erfindung anhand von Ausführungsbeispielen näher erläutert.The invention will be explained in more detail by means of exemplary embodiments.
In der Tabelle 1 ist beispielhaft eine Zusammensetzung eines erfindungsgemäßen Stahls angegeben. Dieser Stahl ist erschmolzen, zu einem Vorblock im Strang vergossen und zu Stäben und Draht warmgewalzt worden. Anschließend sind verschiedene Proben dieses Stahls unterschiedlich schnell abgekühlt worden.Table 1 shows by way of example a composition of a steel according to the invention. This steel has been smelted, cast into a billet in the strand and hot rolled into bars and wire. Subsequently, various samples of this steel have been cooled at different rates.
Die durchgeführten Untersuchungen haben für erfindungsgemäß legierte Stähle folgende Feststellungen ergeben:
- Bei einer von der Austenitisierungstemperatur ausgehenden Abkühlungsgeschwindigkeit von 1 bis 3 K/s wird eine relativ einheitliche Härte von rd. 460 HV erreicht, die einer Zugfestigkeit von umgerechnet 1485 N/mm2 entspricht. Die genannte Abkühlungsgeschwindigkeit entspricht dem Abkühlen von Rundstäben mit einem Durchmesser von 10 bis etwa 30 mm an Luft.
- Bei einer von der Austenitisierungstemperatur ausgehenden relativ langsamen Abkühlungsgeschwindigkeit von 0,5 K/s wird ein martensitisches Gefüge erreicht. Diese Abkühlungsgeschwindigkeit entspricht dem Abkühlen von einem 70 mm Rundstab an ruhender Luft. In diesem Zustand ergibt sich eine Härte von 425 HV, die umgerechnet einer Zugfestigkeit von rd. 1370 N/mm2 entspricht.
- Bei noch langsamerer Abkühlungsgeschwindigkeit von 0,2 K/s wandelt der Stahl in etwa 98 % Martensit mit einem minimalen Anteil von 2 % Ferrit um. Diese Abkühlungsgeschwindigkeit entspricht dem Abkühlen an ruhender Luft von einem 130 mm Rundstab. Die Härte in diesem Zustand liegt um 425 HV (rd. 1300 N/mm2).
- Bei einer von der Austenitisierungstemperatur ausgehenden Abkühlungsgeschwindigkeit von 0,05 K/s wird ein "Duplexgefüge" von rd. 16 % Ferrit und 84 % Martensit mit einer Härte von 360 HV (umgerechnet eine Festigkeit von rd. 1155 N/mm2) eingestellt. Dieses Mischgefüge ist für bestimmte Anwendungen, bei denen eine Randschichtverfestigung z. B. durch Autofrettage vorgenommen wird, sehr vorteilhaft.
- Die Temperatur für die Martensitumwandlung liegt bei rd. 370 °C. Nach dem Umwandeln in die Martensitstufe bei dieser Temperatur ergibt sich bei der anschließenden Abkühlung ein Selbstanlasseffekt. Dieser Selbstanlasseffekt führt zu einer Erhöhung der Zähigkeit des umgewandelten Martensites.
- Ein weiterer Vorteil ist, dass der Beginn der Umwandlung in die Austenitstufe (Ac1b-Temperatur von 739 °C) so hoch liegt, dass dieser Werkstoff durchaus auf unterschiedliche Festigkeiten nach dem Herstellen des Bauteiles angelassen werden kann. Somit ergibt sich ein vielfältiges Spektrum für die Anwendung dieses Stahles bei unterschiedlichen Festigkeiten je nach Bauteilanforderung, ausgehend von einem sehr geeigneten Basisgefüge bestehend aus feinkörnigem und zähem Martensit.
- At a cooling rate of 1 to 3 K / s emanating from the austenitizing temperature, a relatively uniform hardness of approx. 460 HV, which corresponds to a tensile strength of the equivalent of 1485 N / mm 2 . The said cooling rate corresponds to the cooling of round rods with a diameter of 10 to about 30 mm in air.
- At a relatively slow cooling rate of 0.5 K / s emanating from the austenitizing temperature, a martensitic structure is achieved. This cooling rate corresponds to the cooling of a 70 mm rod in still air. In this condition results in a hardness of 425 HV, the equivalent of a tensile strength of approx. 1370 N / mm 2 .
- At an even slower rate of cooling of 0.2 K / s, the steel converts into about 98% martensite with a minimum of 2% ferrite. This cooling rate corresponds to cooling in still air from a 130 mm round rod. The hardness in this state is around 425 HV (about 1300 N / mm 2 ).
- At a cooling rate of 0.05 K / s emanating from the austenitizing temperature, a "duplex texture" of approx. 16% ferrite and 84% martensite with a hardness of 360 HV (equivalent to a Firmness of approx. 1155 N / mm 2 ). This mixed structure is for certain applications in which a surface hardening z. As is done by autofrettage, very beneficial.
- The temperature for the martensite transformation is approx. 370 ° C. After conversion to the martensite stage at this temperature, the subsequent cooling gives rise to a self-priming effect. This self-priming effect leads to an increase in the toughness of the transformed martensite.
- A further advantage is that the beginning of the transformation into the austenite stage (Ac1b temperature of 739 ° C.) is so high that this material can definitely be tempered to different strengths after the component has been manufactured. This results in a diverse spectrum for the application of this steel at different strengths depending on the component requirement, starting from a very suitable basic structure consisting of fine-grained and tough martensite.
In Bild 1 ist das Gefüge des gemäß Tabelle 1 zusammengesetzten erfindungsgemäßen Stahles bei bestimmten Abkühlungsgeschwindigkeiten wiedergegeben. Es handelt sich um ein martensitisches Gefüge, das sehr feinkörnig ausgebildet ist.In Figure 1, the microstructure of the inventive composite according to Table 1 steel is reproduced at certain cooling rates. It is a martensitic structure that is very fine-grained.
Die Festigkeitskennwerte von zwei aus dem erfindungsgemäß gemäß Tabelle 1 zusammengesetzten Stahl erzeugten, jeweils mit einer Abkühlrate von 0,5 K/s abgekühlten Proben 1 und 2 sind in Tabelle 2 wiedergegeben. Mit ihrem feinkörnigen, martensitischen Gefüge haben diese Proben Festigkeitswerte von rd. 1480 bis 1500 N/mm2 in Verbindung mit überraschend hohen Brucheinschnürungswerten von rd. 45 % erreicht.The strength characteristics of two samples 1 and 2 cooled from the steel composite according to the invention according to Table 1, each cooled at a cooling rate of 0.5 K / s, are shown in Table 2. With your fine-grained, martensitic microstructure, these samples have strength values of approx. 1480 to 1500 N / mm 2 in connection with surprisingly high Brucheinschnürungswerten of approx. 45% achieved.
Der erfindungsgemäße Stahl wandelt also durch geeignete Abkühlung von der Austenitisierungstemperatur in die Martensitstufe um und erreicht eine unerwartet gute Kombination von Festigkeit und Bruchverformungskennwerten (Duktilität) wegen der Feinkörnigkeit des Gefüges und des Selbstanlasseffektes während des Abkühlprozesses. Somit können Bauteileigenschaften ohne weitere nachträgliche Wärmebehandlungen eingestellt werden.
Claims (25)
dadurch gekennzeichnet, dass sein Mn-Gehalt 1,6 - 1,8 Gew.-% beträgt.Steel according to one of the preceding claims,
characterized in that its Mn content is 1.6-1.8% by weight.
dadurch gekennzeichnet, dass sein Mo-Gehalt 0,2 - 0,4 Gew.-% beträgt.Steel according to one of the preceding claims,
characterized in that its Mo content is 0.2-0.4% by weight.
dadurch gekennzeichnet, dass sein Nb-Gehalt 0,08 - 0,12 Gew.-% beträgt.Steel according to one of the preceding claims,
characterized in that its Nb content is 0.08 - 0.12 wt .-%.
dadurch gekennzeichnet, dass sein Ti-Gehalt 0,025 - 0,045 Gew.-% beträgt.Steel according to one of the preceding claims,
characterized in that its Ti content is 0.025 - 0.045 wt .-%.
dadurch gekennzeichnet, dass sein Ni-Gehalt max. 0,2 Gew.-% beträgt.Steel according to one of the preceding claims,
characterized in that its Ni content max. 0.2 wt .-% is.
dadurch gekennzeichnet, dass er eine Zugfestigkeit von mindestens 1200 N/mm2 aufweist.Steel according to one of the preceding claims,
characterized in that it has a tensile strength of at least 1200 N / mm 2 .
dadurch gekennzeichnet, dass er eine Brucheinschnürung von mindestens 30 % aufweist.Steel according to one of the preceding claims,
characterized in that it has a Brucheinschnürung of at least 30%.
dadurch gekennzeichnet, dass er ein ferritisch-martensitisches Duplex-Gefüge mit einem Ferrit-Gehalt von 15 - 30 % und einem Martensit-Gehalt von 70 - 85 % aufweist.Steel according to one of the preceding claims,
characterized in that it has a ferritic-martensitic duplex structure with a ferrite content of 15-30% and a martensite content of 70-85%.
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DE102006046481 | 2006-09-29 |
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EP1905857A3 EP1905857A3 (en) | 2010-03-03 |
EP1905857B1 EP1905857B1 (en) | 2013-08-14 |
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Cited By (10)
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WO2010046475A1 (en) * | 2008-10-23 | 2010-04-29 | Deutsche Edelstahlwerke Gmbh | Case-hardened steel |
CN105063514A (en) * | 2015-09-07 | 2015-11-18 | 宁波瑞国精机工业有限公司 | Iron chain pin for vehicles and processing method thereof |
CN105543678A (en) * | 2015-12-21 | 2016-05-04 | 武钢集团昆明钢铁股份有限公司 | Steel wire rod for high-strength boron-contained and annealing-free fastening piece and preparation method thereof |
EP3231879A4 (en) * | 2014-12-08 | 2018-07-18 | NHK Spring Co., Ltd. | Production method for stabilizers |
CN110359007A (en) * | 2019-07-16 | 2019-10-22 | 苏州新凌高强度紧固件有限公司 | A kind of heat treatment method of 20MnTiB fastener |
WO2020058269A1 (en) | 2018-09-18 | 2020-03-26 | Ezm Edelstahlzieherei Mark Gmbh | Steel for surface hardening with high edge hardness and with a fine ductile core structure |
CN112626308A (en) * | 2020-12-25 | 2021-04-09 | 常州东方特钢有限公司 | Production process of high-quality asymmetric flat-bulb steel produced by adding NbN |
CN112795854A (en) * | 2020-12-23 | 2021-05-14 | 石家庄钢铁有限责任公司 | High-strength fastener bolt steel and production method thereof |
US11111554B2 (en) | 2014-12-08 | 2021-09-07 | Nhk Spring Co., Ltd. | Stabilizer |
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WO2010046475A1 (en) * | 2008-10-23 | 2010-04-29 | Deutsche Edelstahlwerke Gmbh | Case-hardened steel |
EP3231879A4 (en) * | 2014-12-08 | 2018-07-18 | NHK Spring Co., Ltd. | Production method for stabilizers |
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US11111554B2 (en) | 2014-12-08 | 2021-09-07 | Nhk Spring Co., Ltd. | Stabilizer |
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CN105543678A (en) * | 2015-12-21 | 2016-05-04 | 武钢集团昆明钢铁股份有限公司 | Steel wire rod for high-strength boron-contained and annealing-free fastening piece and preparation method thereof |
CN105543678B (en) * | 2015-12-21 | 2017-04-05 | 武钢集团昆明钢铁股份有限公司 | High intensity non-annealed steel for fastener wire rod of a kind of boracic and preparation method thereof |
WO2020058269A1 (en) | 2018-09-18 | 2020-03-26 | Ezm Edelstahlzieherei Mark Gmbh | Steel for surface hardening with high edge hardness and with a fine ductile core structure |
CN110359007A (en) * | 2019-07-16 | 2019-10-22 | 苏州新凌高强度紧固件有限公司 | A kind of heat treatment method of 20MnTiB fastener |
CN112795854A (en) * | 2020-12-23 | 2021-05-14 | 石家庄钢铁有限责任公司 | High-strength fastener bolt steel and production method thereof |
CN112626308A (en) * | 2020-12-25 | 2021-04-09 | 常州东方特钢有限公司 | Production process of high-quality asymmetric flat-bulb steel produced by adding NbN |
CN113699437A (en) * | 2021-06-25 | 2021-11-26 | 武汉钢铁有限公司 | Hot continuous rolling dual-phase wear-resistant steel for carriage plate and production method thereof |
Also Published As
Publication number | Publication date |
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EP1905857B1 (en) | 2013-08-14 |
ES2430839T3 (en) | 2013-11-22 |
EP1905857A3 (en) | 2010-03-03 |
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