EP2737097A1 - Stahl, bauteil und verfahren zum herstellen von stahl - Google Patents
Stahl, bauteil und verfahren zum herstellen von stahlInfo
- Publication number
- EP2737097A1 EP2737097A1 EP12741323.5A EP12741323A EP2737097A1 EP 2737097 A1 EP2737097 A1 EP 2737097A1 EP 12741323 A EP12741323 A EP 12741323A EP 2737097 A1 EP2737097 A1 EP 2737097A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- weight
- tantalum
- hrc
- component
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 116
- 239000010959 steel Substances 0.000 title claims abstract description 116
- 238000004519 manufacturing process Methods 0.000 title claims description 13
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 40
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims abstract description 40
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 28
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 28
- 238000005275 alloying Methods 0.000 claims description 32
- 238000000034 method Methods 0.000 claims description 32
- 229910045601 alloy Inorganic materials 0.000 claims description 24
- 239000000956 alloy Substances 0.000 claims description 24
- 239000010955 niobium Substances 0.000 claims description 23
- 238000005096 rolling process Methods 0.000 claims description 22
- 229910052758 niobium Inorganic materials 0.000 claims description 15
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 15
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 11
- 239000011651 chromium Substances 0.000 claims description 11
- 230000006698 induction Effects 0.000 claims description 11
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical group [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 6
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 239000011733 molybdenum Substances 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 239000011572 manganese Substances 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 3
- XTDAIYZKROTZLD-UHFFFAOYSA-N boranylidynetantalum Chemical compound [Ta]#B XTDAIYZKROTZLD-UHFFFAOYSA-N 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- BPUBBGLMJRNUCC-UHFFFAOYSA-N oxygen(2-);tantalum(5+) Chemical compound [O-2].[O-2].[O-2].[O-2].[O-2].[Ta+5].[Ta+5] BPUBBGLMJRNUCC-UHFFFAOYSA-N 0.000 claims description 2
- 229910021332 silicide Inorganic materials 0.000 claims 1
- FVBUAEGBCNSCDD-UHFFFAOYSA-N silicide(4-) Chemical compound [Si-4] FVBUAEGBCNSCDD-UHFFFAOYSA-N 0.000 claims 1
- 229910001936 tantalum oxide Inorganic materials 0.000 claims 1
- 230000008569 process Effects 0.000 description 19
- 239000000463 material Substances 0.000 description 17
- 235000019589 hardness Nutrition 0.000 description 16
- 230000015572 biosynthetic process Effects 0.000 description 14
- 238000010438 heat treatment Methods 0.000 description 11
- 230000001965 increasing effect Effects 0.000 description 9
- 230000003068 static effect Effects 0.000 description 8
- 239000010936 titanium Substances 0.000 description 8
- 239000011575 calcium Substances 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 6
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 description 6
- 229910003468 tantalcarbide Inorganic materials 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 5
- 230000033001 locomotion Effects 0.000 description 5
- 230000002829 reductive effect Effects 0.000 description 5
- 238000005204 segregation Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 238000010276 construction Methods 0.000 description 4
- 230000001939 inductive effect Effects 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000013021 overheating Methods 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 4
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 3
- 229910052791 calcium Inorganic materials 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 210000001061 forehead Anatomy 0.000 description 3
- 230000003313 weakening effect Effects 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 229910000805 Pig iron Inorganic materials 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 125000004122 cyclic group Chemical group 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000005272 metallurgy Methods 0.000 description 2
- 230000002093 peripheral effect Effects 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 229920003023 plastic Polymers 0.000 description 2
- 239000004033 plastic Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910000976 Electrical steel Inorganic materials 0.000 description 1
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 229920000426 Microplastic Polymers 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- MANYRMJQFFSZKJ-UHFFFAOYSA-N bis($l^{2}-silanylidene)tantalum Chemical compound [Si]=[Ta]=[Si] MANYRMJQFFSZKJ-UHFFFAOYSA-N 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 229940043430 calcium compound Drugs 0.000 description 1
- 150000001674 calcium compounds Chemical class 0.000 description 1
- 230000002860 competitive effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000356 contaminant Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001186 cumulative effect Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 230000002500 effect on skin Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 239000003365 glass fiber Substances 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000009847 ladle furnace Methods 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 238000011089 mechanical engineering Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- RHDUVDHGVHBHCL-UHFFFAOYSA-N niobium tantalum Chemical compound [Nb].[Ta] RHDUVDHGVHBHCL-UHFFFAOYSA-N 0.000 description 1
- 230000001473 noxious effect Effects 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000009931 pascalization Methods 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002028 premature Effects 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 238000005476 soldering Methods 0.000 description 1
- 230000002269 spontaneous effect Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000009849 vacuum degassing Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Definitions
- Embodiments of the present invention relate to steel, a structural member having the steel, and a method of manufacturing the steel.
- steel is used on account of its far-reaching manufacturability, its strength, its deformability, its weldability and many other properties.
- One of the most important technological features is that steel can be completely or partially hardened. If, for example, only edge hardening or surface hardening is carried out, then the correspondingly treated surface becomes harder and thus more mechanically and tribologically resistant, while deeper areas of the machine part have lower hardness and thus greater toughness, as a result of which the machine part as a whole becomes cyclically and statically more resilient.
- Dynamic loads are often introduced via the surface of the machine parts in this, so have a strong impact on the typically hardened areas. This can cause dislocation movements in the material, which can ultimately lead to plastic deformation in the interior of the machine part. These often claim the range of grain boundaries in the microstructure of steel, which can lead to an intercrystalline fracture before reaching the strength in volume under susceptible material state.
- the hardening of the steel in the edge region typically takes place thermally, the steel of the machine part being heated accordingly. This can be done for example by flame or induction hardening, so for example by an inductive heating of the workpiece.
- Hardening represents a thermally induced process, so that undesired heating above the austenitic temperature of the steel and thus overheating of the microstructure can occur, especially in the case of relatively large edge hardening depths. As a result, an increased grain growth, so a coarse grain formation occurs. This can lead to reduced strength in the subsequent insert structure due to weakening of the grain boundaries (eg, by segregation, i.e., attachment of noxious elements), with a tendency for intergranular fracture.
- the object of the present invention is therefore to provide a steel which has improved hardenability and / or improved grain stability and / or static strength.
- An exemplary embodiment of a steel comprises tantalum in a proportion of between 0.01 and 2 percent by weight and a carbon content of at least 0.25 percent by weight and at most 1.55 percent by weight.
- One embodiment of a method of making steel includes providing a base alloy of the steel and alloying the base alloy with tantalum such that the steel has tantalum at a level of between 0.01 and 2 percent by weight and a carbon content that is at least 0.25 percent by weight; at most 1.55 weight percent.
- Embodiments of the invention are based on the finding that an improved hardenability and / or improved grain stability and / or static strength can be achieved by using tantalum as a (carbon) steel having a carbon content of at least 0.25% by weight and at most 1.55% by weight. ) Alloying element is added.
- tantalum as a (carbon) steel having a carbon content of at least 0.25% by weight and at most 1.55% by weight.
- Alloying element is added.
- investigations have shown that even very low tantalum levels of about 0.01 percent by weight lead to improved hardenability or to improved grain stability.
- With increasing proportion of tantalum With increasing proportion of tantalum, a corresponding improvement of the abovementioned properties compared to unalloyed steel is achieved in the range between 0.01 and 2.0 per cent by weight.
- the addition of tantalum makes it possible to increase the austenitizing temperature during edge hardening. hereby For example, the accessible process temperatures can be increased to over 1000 ° C, for example up to 150
- Embodiments of the present invention further have for its object to provide a component which has improved fatigue resistance in at least one section.
- An embodiment of the present invention in the form of a component thus comprises in at least a portion of the aforementioned steel, the portion extending from a surface of the component to an interior of the component, and wherein the component has edge hardening in the portion.
- it may extend at least 5 mm into the interior of the component, while in other embodiments, lower or greater edge cure depths may be realized.
- Embodiments of the present invention with respect to this aspect are based on the finding that improved hardenability and / or static strength and / or improved grain stability during the heat treatment during curing can be achieved by the use of the steel described above, or that thereby a process for curing a component can be simplified.
- edge hardening having a greater edge hardening depth of at least 5 mm can be achieved in at least a portion of the component by (eg, inductive) hardening. ne that here an increased coarse grain formation sets in, which could adversely affect the fatigue resistance and static strength of the material.
- embodiments of the present invention are by no means limited to components having an edge hardening depth of 5 mm or more.
- Embodiments of the present invention also include components with a lower edge hardening depth than 5 mm, so for example those with Randhärtungstiefen of at least 100 ⁇ , at least 200 ⁇ , at least 500 ⁇ , at least 1 mm or at least 2 mm.
- nominal weight percentages are used with respect to the individual components.
- deviations from the nominal proportions may occur due to the production-related processes of steel production.
- the proportion of an alloying element or another component (eg carbon) of a steel of a specific embodiment may thus be below or exceeding the nominal values within the scope of the usual manufacturing and manufacturing tolerances.
- Fig. 1 shows a cross section through a tapered roller bearing with components according to embodiments of the present invention
- FIG. 2 shows a schematic cross-sectional view through a component according to an exemplary embodiment of the present invention during edge hardening
- FIGS. 3 illustrates a graph of hardness through a component according to an embodiment of the present invention as a function of a distance from the surface of the component.
- hardened steels are frequently used, in particular surface-hardened steels.
- steels are preferred which have small particle sizes in order to distribute occurring mechanical loads and weakening segregation or precipitation assignments to a large number and thus area of grain boundaries.
- a workpiece In induction hardening or flame hardening, therefore, a workpiece is locally heated to a temperature of more than 1000 ° C frequently by being heated from outside (flame hardening) or by eddy currents (induction hardening) generated in an outer layer of the workpiece near the surface.
- eddy currents induction hardening
- locally temperatures of up to 1 150 ° C can be achieved.
- this can easily lead to overheating of the structure, which in turn can lead to the coarse grain formation described above and thus frequently associated grain boundary segregation and thus to a reduction in the fatigue resistance and static strength of the material and component.
- an improvement in the grain stability and / or the hardenability in the heat treatment can be achieved by the use of a steel which in addition to a proportion of carbon (C) of at least 0.25 weight percent and at most 1.55 weight percent zent a proportion of tantalum (Ta), which is between 0.01 and 2 percent by weight.
- C carbon
- Ta tantalum
- edge hardening depths 10 mm and optionally above this can be achieved.
- embodiments of the present invention are not limited to such components having an edge hardening depth of at least 5 mm. It can be realized in accordance with embodiments of the present invention as well components with lower or larger Randhärtungstiefen, ie, for example, at least 100 ⁇ , at least 1 mm or at least one of the other, here mentioned in the present description possible Randhärtungstiefen.
- Randhärtungstiefen when the carbon content of the steel is reduced to values of at least 0.25 weight percent and at most 1.1 weight percent or even at most 0.6 weight percent, this may eventually result in further improved edge hardenability allowing greater edge cure depths and risk the melting of the microstructure is reduced.
- Variation of the carbon content in the range of between about 0.4 and about 0.55 wt%, for example, about 0.45 wt%, can add additional beneficial properties to the steel, such as improved inductive solderability.
- embodiments of the present invention make it possible to increase the temperatures used for edge curing and thus to reduce the aforementioned risk of coarse grain formation. Due to the use of steels according to As a result of the present invention, if necessary, the temperature required for curing can be increased in the range above 1000 ° C.
- the proportion of the alloying metal is within a range that is typically not specified. In the case of tantalum, this is generally the range below
- alloying is understood to mean both that of microalloying and of alloying.
- Embodiments of the present invention may further comprise an alloying element having a weight fraction between 0, 1 and 5 percent by weight, which may be molybdenum (Mo), nickel (Ni), silicon (Si), manganese (Mn) or chromium (Cr) can.
- the weight fraction is often in the range between 0.8% and 1.5% by weight.
- steel according to an embodiment of the present invention may be produced based on 50CrMo4 or 43CrMo4 as a base alloy. As some of these base alloys also show, in embodiments also a plurality of the aforementioned alloying elements can be used.
- the steel further comprises another alloying element having a weight fraction between 0.01 and 2 percent by weight, the further alloying element being niobium (Nb), titanium (Ti) or vanadium (V).
- the proportion by weight of this further alloying element is often in the range between 0, 1 and 1 percent by weight.
- steels according to embodiments of the present invention based on 50CrV4.
- the proportion by weight of tantalum (Ta) is frequently at least 1 times, at least 5 times, at least 10 times, at least 20 times, at least 50 times, or at least 100 times. times the weight fraction of niobium (Nb).
- a tantalum content of at least 120 times, at least 150 times or at least 200 times the niobium content may also correspond, with these ratios already being very close to the limit of the technical separation possibility of the two elements. Due to the apparently not very detrimental effect of niobium (Nb), it may therefore be more suitable for economic and procurement reasons, and for reasons of actual steel production, to tolerate a certain niobium content in order to simplify the process of steel production and / or to keep it technically more stable ,
- chromium it may be advisable, in embodiments, to limit the chromium content to a maximum of 5% by weight, to a maximum of 3.8% by weight or to a maximum of 2.1% by weight. Thus, this may possibly result in a competitive situation in the formation of carbides or other carbon-containing compounds, complexes or deposits between see tantalum and chrome are suppressed. It may also be advisable to add molybdenum (Mo) by weight up to 0.6% by weight.
- a steel according to an embodiment of the present invention often comprises no other alloying elements (ie excluding carbon) other than iron (Fe) in a respective proportion of more than 0.2 wt.%, Wherein a total proportion of the further elements as a whole 10 wt .-% does not exceed. In purer versions of steels, these limits may also be 0.1 wt .-% and 5 wt .-%.
- a steel is a material whose mass fraction of iron (Fe) is greater than that of any other element whose carbon content is generally less than 2% by weight. % is and can contain other elements.
- Embodiments of the steel have a carbon content that is at least 0.25 weight percent, but does not exceed 1.55 weight percent.
- a sufficient amount of carbon can be provided for carbide formation.
- an increase of the carbon content can be avoided if necessary.
- a steel according to an embodiment may be designed as bearing steel, as defined for example in ISO 683-17: 1999.
- Such an induction hardenable steel based on a 43CrMo4-base alloy according to one embodiment can achieve, for example, one or more hardness values, as listed in Table 1 reproduced below.
- Table 1 shows a minimum H C value (HRC m j n ) for a typical steel alloy and a maximum HRC value (HRC max ) for a typical steel alloy a distance d from a quenched end face in mm opposite each other.
- the hardenability can be measured here by Jominy forehead quenching tests at different end face distances.
- HRC values which are 2 or 3 HRC values above or below the stated minimum and / or maximum HRC values HRC max or HRC min can optionally also be achieved on the basis of the abovementioned base alloy 43CrMo4.
- hardnesses starting from 20 HRC in the case of a steel having a carbon content of 0.25% by weight up to 70 HRC in a steel having a carbon content of 1.55% by weight can be used. be achieved.
- one or more hardness values can be determined according to the following minimum and maximum HRC values HRC m j n or HRC max given in Table 2 as a function of the distance d from the Quenched face in mm can be achieved.
- HRC min and HRC max values can be achievable, which are 2 or 3 HRC levels or values above or below the values given in Table 2 are given.
- the hardenability can also be measured here by Jominy forehead quenching tests at different end face distances.
- steels according to embodiments of the present invention have reduced grain growth in the heat treatment and thus (generally) a small grain size.
- they have microstructures with grains with a score of 5, 6, 7 or more.
- a photo is compared at a magnification of 100: 1 with different standard images.
- the class 5 grains here correspond with a mean diameter of about 60 ⁇ , those of class 6 such with a mean diameter of about 45 ⁇ , those of class 7 such with a mean diameter of about 35 ⁇ and those of class 8 such with a average diameter of about 22 ⁇ .
- the size or grain boundaries of the former austenite grains are referred to as grain size and grain boundaries.
- exemplary embodiments of steels can be quantified using, for example, the measurement methods defined in the standards ASTM E45 and ISO 4967 and DIN 50602: 1985. Even with these methods, cuts are made, and compared with standard images in a magnification of 100: 1. Embodiments may be provided according to the following microstructure classes or better. Table 3 shows nonmetallic inclusions according to ASTM E45 and ISO 4967, which can achieve exemplary embodiments.
- Table 4 shows non-metallic inclusions according to DIN 50602: 1985, which can achieve embodiments.
- bar diameter d in mm is compared with characteristic cumulative K values.
- Steels according to embodiments of the present invention are made in a process comprising two steps that may be performed simultaneously or sequentially.
- a base alloy of the steel is provided in a first step, which is then alloyed with tantalum in a second step.
- steels according to embodiments of the present invention can be produced using all methods, even if due to economic and / or process-related properties, individual methods are used more in peripheral areas.
- the tantalum is added in metallic form, for example in powder form or as granules (pieces), or as a chemical compound.
- tantalum may be added, for example, as tantalum carbide (TaC), tantalum boride (TaB 2 ), tantalum silicide (TaSi 2 ) or tantalum oxide (Ta 2 O 5 ).
- the step of providing the base alloy may include providing pig iron in a blast furnace route, but also by other methods.
- the pig iron can then be further processed into steel by means of a blowing process (eg LD process or Linz-Donawitz process) or a fresh hearth process (eg Siemens-Martin process).
- the provision of the base alloy may further comprise refining resulting in an adjustment (generally a decrease) in the content of elements such as silicon (Si), manganese (Mn), sulfur (S), or even phosphorus (P) ,
- the properties of the base alloy thus produced can optionally be further changed.
- Examples include vanadium (V), chromium (Cr), calcium (Ca), silicon (Si), niobium (Nb), titanium (Ti), nickel (Ni), and molybdenum (Mo).
- deoxidation can be achieved by adding aluminum (AI), silicon (Si), calcium (Ca) or calcium compounds.
- the tantalum can then be added to the base alloy in metallic or chemically bound form.
- the tantalum can in this case be added, for example, in the form of the abovementioned chemical compounds of the base alloy.
- the step of alloying with tantalum is hereby a typical step of secondary metallurgy, which can be carried out, for example, in a ladle furnace process after refining.
- further alloying elements may be added, such as vanadium (V), chromium (Cr), calcium (Ca), silicon (Si), niobium (Nb), titanium (Ti), nickel (Ni), molybdenum (Mo) or other elements, as far as necessary or desired.
- chromium, tantalum and molybdenum can act to inhibit corrosion.
- the step of alloying with tantalum takes place here at a temperature of less than 1600 ° C, where appropriate, the temperature can also be limited to values of below 1550 ° C or below 1500 ° C.
- further process steps may be included, such as degassing by a vacuum degassing or by other methods. This may optionally be followed by further mechanical, thermal or other further processing steps, such as rolling of the steel.
- Fig. 1 shows a cross section through a tapered roller bearing 100 for a large plant, such as a wind turbine, a tidal power plant, a rolling mill or a construction machine.
- the tapered roller bearing 100 comprises an outer ring 110 and an inner ring 120, which are shown in FIG. 1 with respect to a line of symmetry 130, wherein the line of symmetry 130 coincides with the axis of the tapered roller bearing 100.
- a plurality of frustoconical rolling elements 140 is arranged, which are guided by an optional cage 150.
- the rolling elements 140 roll on a running surface 160 of the inner ring 120 and a running surface 170 of the outer ring 1 10 from.
- the tapered roller bearing has 100 guide rims.
- the inner ring thus comprises a first board 180 and a second board 190, while the outer ring shown here has no lateral guide rims.
- the outer ring 1 10 and the inner ring 120 are in this case made entirely of a steel according to an embodiment of the present invention.
- these each have an edge hardening region 200, 210, in which the steel of the two rolling bearing rings 1 10, 120 has been subjected to edge hardening.
- Both edge hardening regions 200, 210 extend from the surfaces of the two components, that is to say the two running surfaces 160, 170, to a peripheral hardening depth that can be predetermined by the process parameters and the material properties of the steel used, into the component.
- the edge hardening regions extending from the surfaces of the components may extend at least 5 mm into them, but may also have lower or greater edge hardening depths.
- a thicker edge hardening range of 10 mm or more can be produced, which counteracts premature fatigue, especially in the case of heavily loaded components, such as the rolling bearing rings of large machines, and also for higher machining allowances for larger rolling bearing rings (eg because of distortion ).
- Randhärtungs Symposiume with Randhärtungstiefen in the extent described are often very welcome for various reasons.
- Both the outer ring 1 10 and the inner ring 120 therefore represent embodiments of a component according to the present invention.
- FIG. 2 illustrates the production of the edge hardening region 200 by means of induction hardening using the example of the outer ring 110 shown in FIG. 1.
- an inductor 220 is guided over the surface to be hardened, that is in the present case over the running surface 170, while the inductor 220 in the workpiece (component or outer ring 1 10) generates eddy currents via an alternating magnetic field.
- the inductor 220 comprises a coil, not shown in FIG. 2, by means of which an alternating current with a predetermined, adjustable or programmable frequency can be added.
- the current intensity of the current ie substantially the power of the inductor 220
- a certain amount of heat by electrical current flow and heat conduction in a surface layer of the workpiece 1 10th may optionally also include a cooling system, not shown in FIG. 2, that is to say a water cooling system.
- a penetration depth of the alternating field and thus a thickness of the edge hardening area to be generated can be determined via the frequency.
- a quantity of heat can thus be introduced into the workpiece (outer ring 10) under its surface (tread 170), through which it can be introduced the thermally induced hardening of the steel.
- edge hardening region 170 Due to the effect of heat, formation of the structure then occurs in the edge hardening region 170, but because of the use of the steel according to embodiments of the present invention, coarse grain formation in the austenite with large martensite needles or slats and corresponding former austenite grain boundaries arising during quenching is essentially prevented, at least however can be reduced, so that the aforementioned thicknesses of the edge hardening areas can be achieved at least without excessive material damage (eg coarse grain with grain boundary segregation).
- inductor 220 for example, temperature increases of more than 100 ° C / s and above can be generated. Studies have shown that with temperature increases between 100 ° C / s and 300 ° C / s grains with an ASTM characteristic of 5 or more, possibly even 6 or 7 and more in the edge hardening range 200 can be achieved.
- Steels according to the embodiments of the present invention are so inductively curable and can be made high strength by such a cure at least in the edge region. They are therefore suitable as steels for rolling bearings and for other applications in which the components made from them are subjected to strong dynamic and / or static loads.
- Rolling bearings are typically cyclic and / or static compressive, with improved hardenability and grain stability counteracting wear, fatigue and spontaneous failure.
- the absence of critical tensile stresses and the high hydrostatic pressure in Hertzian contact cause the hardened steel to flow in a microplastic manner and lead to an order of magnitude greater fatigue life due to rolling over orders of magnitude than a comparable cyclic tensile, compressive or circumferential bending stressing.
- a multi-frequency method can optionally also be used.
- the receptacle for the workpiece (outer ring 110), not shown in FIG. 2, can optionally be grounded in order to improve the heating by the eddy currents thrown in the workpiece.
- the inductor 220 can in this case be operated, for example, with a frequency in the range between 1 kHz and 5 kHz at a distance of less than 20 mm from the surface to be hardened (raceway or running surface 170 and 160). The current or power to be used depends strongly on the geometry and size of the component.
- the hardness initially has a first constant value in the edge hardening region 200 before it decreases outside of the edge hardening region 200 and strives for a second value in the interior of the workpiece.
- the first value of the hardness H is hereby higher than that of the second value, whereby the first value is due to the edge hardening carried out and the second value to the properties of the underlying steel.
- the first value is therefore determined by the hardenability of the steel.
- the hardness can be specified, for example, according to Rockwell according to the HRC scale. Depending on the steel used according to embodiments of the present invention, hardnesses starting from 20 HRC in the case of a steel having a carbon content of 0.25% by weight up to 70 HRC in a steel having a carbon content of 1.55% by weight can be used. be achieved.
- the hardenability can be measured here by Jominy forehead quenching tests at different end face distances.
- the resulting hardness is mainly caused by the carbon content, the range of 0.25 wt .-% to 1.55 wt .-% for the induction hardening tion and the flame hardening is suitable.
- the other alloying metals improve hardenability and prevent excessive grain growth, even a small proportion of tantalum of 0.01% by weight and above, which is attributable to the micro-alloying, has a grain-stabilizing effect. This also applies to higher tantalum contents in the range between 0.1 wt .-% and 2 wt .-%.
- the structure of the steel can be kept largely stable with a high resulting hardness even in the case of a longer and / or higher-temperature heat treatment.
- the tantalum level may also be at least 0.2 weight percent or 0.25 weight percent.
- the tantalum component can also be increased beyond the aforementioned values. For example, if this is increased to values of at least 0.5 percent by weight, in addition to grain refinement, carbide formation or carbide formation may also be positively influenced.
- the material becomes more tolerant to overheating during induction hardening due to microalloying. This expands the available process window and makes the process less susceptible to deviations.
- the inner ring 1 10 and the outer ring 120 of a single row tapered roller bearing shown in Fig. 1 have been described.
- embodiments of the present invention are by no means limited thereto.
- the embodiments also include other types of rolling bearings, such as cylindrical roller bearings, roller bearings, ball bearings, four-point bearings and needle roller bearings as well, such as slide bearings, intermediate rings and other construction and machine parts of rotary and linear bearing technology.
- components of other disciplines of vehicle and mechanical engineering can be implemented as embodiments of the present invention. In principle, this includes all components which have at least one region which is subjected to an increased load, so that it makes sense to carry out a corresponding edge hardening starting from the edge of the relevant component.
- a component according to an exemplary embodiment of the present invention thus has at least one section Steel according to an embodiment of the present invention.
- the portion extends from a surface of the component into an interior of the component, the component having edge hardening in the portion.
- edge hardening extends at least 5 mm into the interior of the component.
- larger or smaller edge hardening depths may also be implemented, as previously described.
- Examples thereof are composite components having a correspondingly shaped portion in which steel according to an embodiment of the present invention is implemented together with a corresponding edge hardening area.
- Other areas of the component in question can be made, for example, from another metal, another alloy or another steel.
- a connection can be made in these cases, for example, cohesively in the form of a solder or welded connection.
- connection methods are conceivable here, for example, a non-positive or positive connection or a bond as another form of cohesive connection. These methods can be used, for example, when soldering or welding is out of the question, ie if the substances involved are not solderable or weldable. Examples of this may be plastics or glass fiber reinforced materials.
- this may extend from the surface along a straight line such that the straight line runs completely in the steel until it reaches a (further) Surface section emerges from the component.
- the component or its section comprising the steel may optionally comprise further materials.
- a component can also be made entirely or in a corresponding section of a material which comprises the steel.
- a material may include, for example, a fiber reinforced steel or other hybrid material combination using steel according to one embodiment.
- a steel according to one embodiment may thus be, for example, a steel for flame or induction hardening. It may alternatively or additionally be a rolling bearing steel. In the case of a steel according to an embodiment, this can have no further elements with a respective proportion of more than 0.2 percent by weight, except for iron and carbon and the abovementioned alloying materials, with a total proportion of the further elements not exceeding 10 percent by weight.
- an improved and / or lighter edge hardening may optionally be achievable.
- exemplary embodiments of the present invention are, first of all, all large plants in which individual components are subjected to a corresponding mechanical stress which renders edge hardening advisable. These include wind and tidal power plants as well as generators, construction machinery, cranes, excavators, vans, trains, aircraft, rolling mills and other machinery. In principle, it may also be advisable to use embodiments in smaller systems and their components, since even in such systems, for example, by sudden shock loads high stresses may occur. Micro-alloyed grain stable steels for inductive heat treatment according to embodiments of the present invention, as well as corresponding components, are therefore applicable in a wide field of applications.
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Abstract
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DE102011079955.9A DE102011079955B4 (de) | 2011-07-28 | 2011-07-28 | Stahl, Bauteil und Verfahren zum Herstellen von Stahl |
PCT/EP2012/064806 WO2013014280A1 (de) | 2011-07-28 | 2012-07-27 | Stahl, bauteil und verfahren zum herstellen von stahl |
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EP2737097A1 true EP2737097A1 (de) | 2014-06-04 |
EP2737097B1 EP2737097B1 (de) | 2020-01-22 |
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EP12741323.5A Active EP2737097B1 (de) | 2011-07-28 | 2012-07-27 | Stahl, bauteil und verfahren zum herstellen von stahl |
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EP (1) | EP2737097B1 (de) |
DE (1) | DE102011079955B4 (de) |
WO (1) | WO2013014280A1 (de) |
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US10837488B2 (en) | 2018-07-24 | 2020-11-17 | Roller Bearing Company Of America, Inc. | Roller bearing assembly for use in a fracking pump crank shaft |
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DE1608155B1 (de) * | 1967-12-16 | 1970-07-02 | Carl Clarus | Verwendung eines Stahles im vergueteten Zustand fuer Hochleistungsketten |
SE330900C (sv) | 1968-05-31 | 1978-12-07 | Uddeholms Ab | Sett att vermebehandla band eller plat av rostfritt, herdbart kromstal |
CA1028935A (en) | 1973-12-14 | 1978-04-04 | Niels N. Engel | Superhard martensite and method of making same |
JPH07216448A (ja) * | 1994-02-04 | 1995-08-15 | Daido Steel Co Ltd | 結晶粒粗大化防止鋼の製造方法 |
JP3411085B2 (ja) | 1994-04-15 | 2003-05-26 | 川崎製鉄株式会社 | 繰り返し応力負荷によるミクロ組織変化の遅延特性に優れた軸受部材 |
JP2000026939A (ja) | 1998-07-13 | 2000-01-25 | Daido Steel Co Ltd | 軸受鋼 |
JP4375971B2 (ja) * | 2003-01-23 | 2009-12-02 | 大同特殊鋼株式会社 | 高強度ピニオンシャフト用鋼 |
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2011
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DE102011079955A1 (de) | 2013-01-31 |
DE102011079955B4 (de) | 2023-10-19 |
WO2013014280A1 (de) | 2013-01-31 |
EP2737097B1 (de) | 2020-01-22 |
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