• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    14 ABSTRACT There is provided a steel with the composition: C: 0.05-0.30 wt°/>, Ni: 3-9 wt°/>, l/lo:0.5-1.5 wt%, Al: 1-3 wt°/>, Cr: 2-14wt°/>, V: 0.25-1.5 wt%, and remaining part up to100 wt°/> is Fe and impurity elements, with the additional proviso that the amountsof Al and Ni also fulfil Al = Ni/2.2 i 0.2 in wt°/>. There is the possibility to have verylow amounts of cobalt. The steel displays, low segregation, high yield strength atelevated temperatures, high resistance against corrosion, and can also suitably benitrided. The steel is more economical to manufacture compared to steel according to the state of the art with the same strength at elevated temperatures.
    公开号:SE1650764A1
    申请号:SE1650764
    申请日:2016-06-01
    公开日:2017-12-02
    发明作者:Andersson Jan-Erik
    申请人:Ovako Sweden Ab；
    IPC主号:
    专利说明:

    [1] [0001]The present invention relates generally to high strength steel suitable foruse at elevated temperature. The steel composition is optimized to give bothprecipitation hardening with carbides together with an inter-metallicprecipitation of Ni-Al present after tempering. The new steel is designed tohave a low micro and macro segregation. lt is possible to provide a steel whichis essentially cobalt free.
    [2] [0002] Primary hardening is when the steel is quenched from the austenitic phasefield into a martensitic or bainitic microstructure. Generally steels comprisingcarbides are known. Low alloy carbon steels generates iron carbides duringtempering. These carbides coarsen at elevated temperatures which reducesthe strength of the steel. When steels contain strong carbide forming elementssuch as molybdenum, vanadium and chromium, the strength can be increasedby prolonged tempering at elevated temperatures. This is due to that alloyedcarbides will precipitate at certain temperatures. Normally these steels reducetheir primary hardened strength when tempered at 100°C to 450°. At 450 °C to550 °C these alloyed carbides precipitate and increase the strength up to oreven higher than the primary hardness, this is called secondary hardening. ltoccurs since the alloying elements (such as molybdenum, vanadium andchromium) can diffuse during prolonged annealing to precipitate finelydispersed alloy carbides. The alloy carbides found in secondary hardenedsteels are thermodynamically more stable than iron carbides and show littletendency to coarsen. Tempering characteristics for various steels can be seen in figure 1.
    [3] [0003] Inter metallic precipitation hardening steels are also known. Both thecarbide precipitation and inter metallic precipitation hardening relies onchanges in solid solubility with temperature to produce fine particles of animpurity phase, which impede the movement of dislocations, or defects in a crystal |attice. Since dislocations are often the dominant carriers of plasticity,this serves to harden the material. Precipitation hardening steels may for instance comprise aluminum and nickel, forming the impurity phase.
    [8] [0008] Every steel grade will segregate more or less depending on steelcomposition. Numerous of steel grades have been examined for the variationsof chemical compositions. The various elements in normal steelmaking and thetendency to segregate can be seen in figure 2. The higher the value of thesegregation index, the more it will segregate. Carbon has an enormousinfluence on the partitioning of various carbide forming elements, such as l/loCr and V. The higher the carbon content, the more segregation will occur. Bothon a micro and a macro scale. Carbon will be restricted to [OOO9]l/l-5O steel is often refined using vacuum-induction melting (Vll/l) andvacuum-arc remelting (VAR) processes, and it exhibits excellent resistance tomulti-axial stresses and softening at high service temperatures as well as goodresistance to oxidation. However it suffers from segregation, as can be seen infigure 3, which would be desirable to avoid. Further it is fairly expensive to manufacture.
    [12] [0012]ln a first aspect there is provided a steel with the composition:C: 0.05-0.30 wt% Ni: 3-9 wt% l/lo: 0.5-1.5 wt% Al: 1-3 wt% Cr: 2-14 wt% V: 0.25-1.5 wt% remaining part up to 100 wt% is Fe and impurity elements, ,with the additional proviso that the amounts of Al and Ni also fulfil Al = (Ni/2.2) i in Wto/o.
    [13] [0013]This is because the optimum usage of Ni and Al will be according to their atomic masses when precipitates of Ni and Al are formed.
    [14] [0014]ln a second aspect there is provided a method of manufacturing a part ofthe steel described above characterized in that the steel is tempered at 510- 530°C to obtain precipitates comprising Ni and Al.
    [15] [0015]ln a third aspect there is provided use of the as described above forapplications where the steel is subjected to a temperature during use from 250to 300°C. ln an alternative embodiment there is provided use of the steeldescribed above for applications where the steel is subjected to a temperatureduring use from 300 to 500°C. ln yet another embodiment there is provided useof the steel as described above for applications where the steel is subjected to a temperature during use from 250 to 500 °C
    [16] [0016]Further aspects and embodiments are defined in the appended claims.
    [17] [0017]One advantage is that the steel can be provided with only trace amounts ofundesired cobalt. lt is possible to use cobalt levels well below 0.01 wt%. Theamounts are so low that any undesired effects are avoided. Low amounts ofcobalt are preferred because of the environmental and health problemsassociated with cobalt.
    [18] [0018]Another advantage is that the strength at elevated temperatures isincreased. Elevated temperatures where the strength is increased are typically250-300 °C or even up to 500 °C. ln one embodiment the upper temperaturelimit for the suitable use of the steel is 450 °C.
    [19] [0019]The steel is more economical to manufacture compared to present steelswith the same strength at elevated temperatures. The steel according to theinvention has the same strength at 250 °C as steel 4 in Fig 4, steel 4 is l/l50,which is more expensive to manufacture since a different and more expensive process, such as remelting using ESR or VAR is required.[0020]Yet another advantage is that the steel is suitable for nitriding.
    [21] [0021]The invention is now described, by way of example, with reference to theaccompanying drawings, in which:
    [22] [0022]Fig. 1 shows the tempering hardness after tempering at 520°C as a functionof tempering time. The steel according to the invention is compared to twoother steels. The hardness HV10 is determined using a calibrated hardnesstester KB30S. The amounts of elements in the different steels in the table are given in wt°/>.
    [23] [0023]Fig. 2 shows various elements in normal steelmaking (Cr, l/lo, and V) andtheir tendency to segregate for different ranges of carbon. The steelcompositions 1-8 disclosed in the table in Fig 2 are the steel compositions forwhich the segregation index has been measured and calculated in Fig 2.
    [28] [0028] Before the invention is disclosed and described in detail, it is to beunderstood that this invention is not limited to particular compounds,configurations, method steps, substrates, and materials disclosed herein assuch compounds, configurations, method steps, substrates, and materials mayvary somewhat. lt is also to be understood that the terminology employedherein is used for the purpose of describing particular embodiments only and isnot intended to be limiting since the scope of the present invention is limitedonly by the appended claims and equivalents thereof.
    [30] [0030]lf nothing else is defined, any terms and scientific terminology used hereinare intended to have the meanings commonly understood by those of skill in the art to which this invention pertains.
    [31] [0031]Essentially cobalt free and similar expressions mean that only traceamounts of cobalt are present. ln one embodiment essentially cobalt free is anamount below a suggested threshold for cobalt of 0.01 wt°/>.
    [32] [0032]All percentages are calculated by weight, unless otherwise clearly indicated.
    [33] [0033]ln a first aspect there is provided a steel with the composition:C: 0.05-0.30 wt% Ni: 3-9 wt% l/lo: 0.5-1.5 wt% Al: 1-3 wt% Cr: 2-14 wt% V: 0.25-1.5 wt% remaining part up to 100 wt% is Fe and impurity elements, ,with the additional proviso that the amounts of Al and Ni also fulfil (Al = Ni/2.2) i in Wto/o.
    [34] [0034]The ratio of Al and Ni is selected because the optimum usage of Ni and Alwill be according to their atomic masses when precipitates of N: Al is formed.
    [35] [0035]ln one embodiment the amount of Cr is in the interval 2-10 wt°/>.
    [36] [0036]ln one embodiment the amount of Co less than 0.03 wt%. ln one embodiment the amount of Co less than 0.02 wt%. ln another embodiment the amount of Co is less than 0.01 wt°/-.~. lt has been proposed that cobalt shouldbe labelled as carcinogenic category 1 B H350 with a specific concentrationlimit (SCL) of 0.01 wt°/>, i.e. a cobalt content of more than 0.01 wt% couldpotentially be harmful. A low cobalt content is desired and in yet anotherembodiment the amount of Co is less than 0.005 wt°/-.~. lt is an advantage of theinvention that it is possible to have a very low amount of cobalt while thedesired properties remain. The amount of cobalt is or can at least be made solow that the steel can be called cobalt free. The low amount of cobalt does notgive impaired properties in other respects such as mechanical properties orstrength at high temperature.
    [37] [0037]ln one embodiment the steel comprises a first type of precipitationscomprising Al and Ni and a second type of precipitations comprising carbidesof at least one selected from the group consisting of Cr, l/lo and V. The twotypes of precipitations give improved mechanical properties.
    [38] [0038]ln a second aspect there is provided a method of manufacturing a part ofthe steel as described above wherein the steel is tempered at 510-530°C toobtain precipitates comprising Ni and Al. This gives the precipitationscomprising Al and Ni. ln one embodiment the steel is tempered at 520°C. lnanother embodiment the steel is tempered at 520°C i 2%. ln one embodimentthe steel is tempered for 1-8 hours. ln one embodiment the steel is temperedfor 6-8 hours. ln yet another embodiment the steel is tempered at 6 hours i 0.5 hours.
    [39] [0039]ln one embodiment the steel is machined before the tempering. This has theadvantage that the steel has lower strength before the tempering compared toafter the tempering and is thereby easier to machine before the temperingcompared to after the tempering. The increase in hardness during tempering at520 °C can be seen in fig 1. For a steel that has essentially the same contentexcept for Al (steel1), there is virtually no increase in hardness , whereas for asteel according to the invention an increase in hardness can be seen reaching a maximum around 6 hours. The increase in hardness is attributed to the formation of precipitates comprising Ni and Al. Steel with either secondary hardening elements g Ni-Al addition has limited hardness after tempering at520 °C (steel2).
    [40] [0040]ln one embodiment solution treatment is carried out before the tempering. lnone embodiment the solution treatment is carried out in the temperatureinterval 900-1000°C during 0.2-3h.
    [41] [0041]ln one embodiment the fatigue limit according to ASTM 468-90 at 250°C ismore than 700 lVlPa. From fig 4 it can be seen that a steel according to theinvention has the same fatigue limit at 250 °C as AlSll/l50 (steel 4). Howeverthe AISA l/l50 steel has high segregation whereas the invented steel has low segregation as seen in fig 3.
    [42] [0042]ln a third aspect there is provided use of the as described above forapplications where the steel is subjected to a temperature during use from 250to 300°C. ln an alternative embodiment there is provided use of the steeldescribed above for applications where the steel is subjected to a temperatureduring use from 300 to 500°C. ln yet another embodiment there is provided useof the steel as described above for applications where the steel is subjected toa temperature during use from 250-500°C. ln a further embodiment there isprovided use of the steel as described above for applications where the steel issubjected to a temperature during use from 250-450°C. From figs 4 and 5 itcan be seen that the fatigue limit and the yield strength is high also at elevated 116m pGFatU TGS.
    [43] [0043]The formula Al = Ni/2.2 i 0.2 should be used with the amounts of Al and Niexpressed in weight percent. The formula gives an additional condition to befulfilled together with all other conditions. Assuming that Ni = 9 wt°/>, then thisformula gives that Al = 4.0909...i 0.2 wt°/>. However there is also the conditionthat the amount of Al is 1-3 wt°/>. The latter condition shall in the presentdisclosure be interpreted so that if the first formula gives an amount of Al whichis 3wt°/> or higher, then 3wt°/> Al should be used. The two conditions taken together give that the amount of Al should be 3 wt°/> in this particular example. lf the endpoint of the Al interval (i.e. 3 wt°/>) is reached the maximum value ofthat element should be selected (i.e. 3wt°/> Al). Thus the formula gives anadditional condition which should be applied together with the other conditionsregarding the amounts of Al and Ni. Both conditions shall be applied. Thecomposition should be chosen so that a solution treatment is possible in theaustenitic phase field. Cr, Al, and l/lo stabilizes ferrite whereas l/ln and Nistabilizes austenite. The invented steel secures an austenitic phase field suitable for hardening.
    [44] [0044]Assuming that Ni = 6.5 wt°/>, then this formula gives that Al = 2.9545...i 0.2wt°/>. However there is also the condition that the amount of Al is 1-3 wt°/>.These conditions together give that Al should be between 2.7545... and 3 wt°/>. l.e. with one decimal between 2.8 and 3.0 wt°/>.
    [45] [0045]The term "impurity elements" is used to include, in addition to iron in thebalance of the alloy, small amounts of impurities and incidental elements,which in character and/or amount do not adversely affect the advantageousaspects of the steel alloy. The bulk of the alloy may contain certain normallevels of impurities, examples include but are not limited to up to about 30 ppmeach of nitrogen, oxygen and sulfur. ln addition the steel according to theinvention comprises l/ln: 0-0.3 wt°/> and Si: 0-0.15 wt°/> or even l/ln: 0-0.5 wt°/>and Si: 0-0.3 wt°/>, however the mentioned concentrations of l/ln and Si do notadversely affect the properties of the steel to a noticeable extent. l/ln and Si are common elements in steel in low concentrations.
    [46] [0046]The precipitation-hardening process can be proceeded by solutiontreatment, or solutionizing, is the first step in the precipitation-hardeningprocess where the alloy is heated above the solidus temperature until a homogeneous solid solution is produced.
    [47] [0047]The corrosion properties are improved. According to a corrosion testperformed according to VDA 233-102 the corrosion properties are better for theinvented steel compared to 100Cr6 (steel1). The data is shown in fig 6. 11 [OO48]Nitriding is a heat treating process that diffuses nitrogen into the surface of ametal to create a case-hardened surface. The content of Cr, l/lo and Al makesthe steel suitable for nitriding. The nitriding is suitably used for furtherimproving the mechanical properties. ln one embodiment nitriding of the steel is carried out.
    [OO49]All the described alternative embodiments above or parts of an embodimentcan be freely combined without departing from the inventive idea as long as thecombination is not contradictory.
    [OO50]Other features and uses of the invention and their associated advantageswill be evident to a person skilled in the art upon reading the description andthe examples.
    [OO51]lt is to be understood that this invention is not limited to the particularembodiments shown here. The embodiments are provided for illustrativepurposes and are not intended to limit the scope of the invention since thescope of the present invention is limited only by the appended claims andequivalents thereof.
    权利要求:
    Claims (16)
    [1] 1. A steel with the composition: C: 0.05-0.30 wt% Ni: 3-9 wt% l/lo: 0.5-1.5 wt% Al: 1-3 wt% Cr: 2-14 wt% V: 0.25-1.5 wt% remaining part up to 100 wt% is Fe and impurity elements, ,with the additional proviso that the amounts of Al and Ni also fulfil Al = Ni/2.2 i 0.2 in wt°/°.
    [2] 2. The steel according to claim 1, wherein the amount of Cr is in theinterval 2-10 wt°/>.
    [3] 3. The steel according to any one of claims 1-2, wherein the amount of Coless than 0.03 wt°/>.
    [4] 4. The steel according to any one of claims 1-2, wherein the amount of Coless than 0.01 wt°/>.
    [5] 5. The steel according to any one of claims 1-4, wherein the steelcomprises a first type of precipitations comprising Al and Ni and a second type ofprecipitations comprising carbides of at least one selected from the groupconsisting of Cr, l/lo and V.
    [6] 6. The steel according to any one of claims 1-5, wherein the fatigue limitaccording to ASTM 468-90 at 250 °C is more than 700 lVlPa 13
    [7] 7. The steel according to any one of claims 1-6, wherein the steel isnitrided.
    [8] 8. A method of manufacturing a part of the steel according to any one of the claims 1-7 characterized in that the steel is tempered at 51 O-530°C to obtainprecipitates comprising Ni and Al.
    [9] 9. The method according to claim 8, wherein the steel is tempered for 1-8hours.
    [10] 10. The method according to claim 8, wherein the steel is tempered for 6-8hours.
    [11] 11. The method according to any one of claims 8-10, wherein the steel is machined before the tempering.
    [12] 12. The method according to any one of claims 8-11, wherein solutiontreatment is carried out before the tempering.
    [13] 13. The method according to claim 12, wherein the solution treatment iscarried out in the temperature interval 900-1000°C during 0.2-3h.
    [14] 14. The method according to any one of claims 8-13, wherein nitriding iscarried out.
    [15] 15. Use of the steel according to any one of claims 1-7 for applications where the steel is subjected to a temperature during use from 250 to 500°C.
    [16] 16. Use of the steel according to claim 15 for applications where the steel issubjected to a temperature during use from 250 to 300°C.
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    引用文献:
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    法律状态:
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