WO2014031053A1

WO2014031053A1 - Method for heat treating a steel component and a steel component

Info

Publication number: WO2014031053A1
Application number: PCT/SE2013/000127
Authority: WO
Inventors: Staffan Larsson; Walter DATCHARY; Isabella FLODSTRÖM; Peter Neuman
Original assignee: Aktiebolaget Skf (Publ)
Priority date: 2012-08-21
Filing date: 2013-08-19
Publication date: 2014-02-27
Also published as: EP2888379B1; JP2015533931A; CN110241378A; EP2888379A1; US9828664B2; CN104781427A; US20150225835A1; EP2888379A4

Abstract

Method for heat treating a steel component (34, 36, 38, 40), which comprises the steps of: a) carbonitriding the steel component (34, 36, 38, 40), and b) ferritically nitrocarburizing the steel component (34, 36, 38, 40).

Description

Method for heat treating a steel component and a steel component TECHNICAL FIELD

The present invention concerns a method for heat treating a steel component, and a steel component that has been subjected to such a method.

BACKGROUND OF THE INVENTION

Carbonitriding is a metallurgical surface modification technique that is used to increase the surface hardness of a metal component, thereby reducing the wear of the component during use. During the carbonitriding process, atoms of carbon and nitrogen diffuse interstitially into the metal, creating barriers to slip and increasing the hardness near the surface, typically in a layer that is 0.1 to 0.3 mm thick. Carbonitriding is usually carried out a temperature of 850-860 °C.

Carbonitriding is normally used to improve the wear resistance of steel components comprising low or medium carbon steel, and not high carbon steel. Although steel components comprising high carbon steel are stronger, they have been found to be more susceptible to cracking in certain applications. Components may for example be used in typically dirty environments where lubricating oil is easily contaminated, such as in a gear box, and it is well known that the service life of components can decrease considerably under such conditions. Particles in the lubricant can namely get in between the various moving parts of a gear box, for example, and make indentations in their contact surfaces. Stress is concentrated around the edges of these indentations and the contact stress concentrations may eventually lead to fatigue cracking. Using components damaged in this way may also result in an increase in the noise generated by the components. Ferritic nitrocarburizing is a surface hardening process in which nitrogen and carbon are supplied to the surface of a ferrous metal. It is usually carried out at a temperature of 525 °C to 625 °C, and produces a thin, hard case consisting of a ceramic iron-nitrocarbide layer (compound layer) and an underlying diffusion zone where nitrogen and carbon are dissolved in the matrix. Ferritic nitrocarburizing is most commonly used on low-carbon, low-alloy steels. SUMMARY OF THE INVENTION

An object of the invention is to provide an improved method for heat treating a steel. This object is achieved by a method that comprises the steps of a) carbonitriding the steel component, and b) ferritically nitrocarburizing the steel component, whereby these steps are preferably carried out sequentially.

Changing the microstructure of the surface of the steel component using such a method improves its wear resistance, corrosion resistance, load bearing capacity, surface hardness, core hardness, compound layer thickness, abrasive wear resistance, adhesive wear resistance, and/or fatigue resistance and enhances its ability to relax stress concentration at the edges of any indentations in its surface. The surface of a steel component subjected to such a method may be provided with a surface hardness of 800-1000 HV, and a core hardness of 300-500 HV depending on the type of steel used. Compared with the prior art, the hardness of both the surface and the core of a high carbon steel component subjected to such a method is greater than that of known components comprising steel having a low carbon content. The wear resistance and fatigue strength for rolling contact are improved as a result. Furthermore, the loading capacity of a steel component, such as a bearing, will be increased, whereby the bearing may be of smaller construction for a particular application. The fatigue resistance on rolling contact also increases, so that the service life of the steel component can be extended. Additionally, the disadvantage that through cracking occurs, described in the prior art, is not found.

The steel component may be provided with a compound layer having a thickness of 10- 20 μηι measured from the surface of the steel component. According to an embodiment of the invention step b) is carried out at a temperature of 500-700 °C, preferably at a temperature below 590 °C. This low process temperature induces little shape distortion in the steel component, which means that post-grinding is not necessary. The method is therefore a cost-efficient way of increasing the wear and corrosion resistance of a steel component. According to an embodiment of the invention step b) may be carried out using gaseous, salt bath, ion or plasma or fluidized bed ferritic nitrocarburizing.

According to an embodiment of the invention the steel component comprises steel with a 5 carbon content of 0.60 to 1.20 weight %, i.e. steel with a medium to high carbon content. According to an embodiment of the invention the steel component comprises a high carbon bearing steel such as SAE 52100/100Cr6 or ASTM-A485 grade 2.

According to a further embodiment of the invention the steel component comprises a 10 100Cr6 steel or a 100CrMo7 steel or any other steel in accordance with ISO 683-17: 1999.

According to an embodiment of the invention the steel component comprises or constitutes a rolling element or roller, or a steel component for an application in which is subjected to alternating Hertzian stresses.

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According to an embodiment of the invention step b) is carried out in an atmosphere of 60% NH₃, 35% N₂ and 5% C0₂.

According to another embodiment of the invention step a) comprises carbonitriding the 20 steel component for 5-25 hours.

According to a further embodiment of the invention the method comprises the step of tumbling the steel component after step b), although not necessarily directly after step b). Tumbling a steel component after ferritic nitrocarburizing provides a finer surface finish 25 and can be used to further improve the fatigue resistance of the steel component.

According to an embodiment of the invention the method comprises the steps of c) quenching the steel component and d) tempering the steel component. Step d) may be carried out at a temperature of 150-260 °C.

30

The present invention also concerns a component made of steel that has a surface hardness of 800-1000 HV and a core hardness of 300-500 HV. Such a steel component may be produced using a method according to any of the embodiments of the invention.

35 According to an embodiment of the invention the steel comprises a compound layer having a thickness of 10-20 μηη. According to another embodiment of the invention the steel has a carbon content of 0.60 to 1.20 weight %. According to a further embodiment of the invention the steel comprises a 100Cr6 steel or a 100CrMo7 steel.

According to an embodiment of the invention the steel component comprises or constitutes a rolling element or roller, or a steel component for an application in which is subjected to alternating Hertzian stresses, such as rolling contact or combined rolling and sliding, such as a slewing bearing or a raceway for a bearing. The component may include or constitute gear teeth, a cam, shaft, bearing, fastener, pin, automotive clutch plate, tool, or a die. The steel component may for example constitute at least part of a roller bearing, a needle bearing, a tapered roller bearing, a spherical roller bearing, a toroidal roller bearing or a thrust bearing. The component may be used in automotive wind, marine, metal producing or other machine applications which require high wear resistance and/or high corrosion resistance and/or increased fatigue and/or tensile strength. BRIEF DESCRIPTION OF THE DRAWINGS

The present invention will hereinafter be further explained by means of non-limiting examples with reference to the appended figures where;

Figure 1 shows a method according to an embodiment of the invention,

Figure 2 shows Micro Vickers hardness profiles of five steel materials that have been subjected to different heat treatments,

Figure 3 shows the corrosion attack on six different materials subjected to different heat treatments,

Figure 4 shows a micrograph of 100Cr6 steel carbonitrided for 8 hours and ferritically nitrocarburized, Figure 5 shows a micrograph of 100Cr6 steel carbonitrided for 22 hours and ferritically nitrocarburized, and

Figure 6 shows a steel component according to an embodiment of the invention.

It should be noted that the drawings have not been drawn to scale and that the dimensions of certain features have been exaggerated for the sake of clarity.

DETAILED DESCRIPTION OF EMBODIMENTS

Figure 1 shows a heat treatment cycle according to the present invention. A steel component is subjected to a carbonitriding process (step a)), at a temperature of 970 °C for 5-25 hours for example. The process environment is for example provided by the introduction of methane/propane/natural gas (for carbon) and ammonia (for nitrogen) into a furnace in the presence of a controlled carrier gas. By maintaining the proper ratios of the working gases, the component is provided with a thin carbonitrided layer of carbon- and nitrogen-rich steel. According to an embodiment of the invention the method includes supplying a higher concentration of ammonia at the beginning of the carbonitriding step a) to boost the carbonitriding process. For example, 9.5% ammonia may be used initially; this may be lowered to 6.5% ammonia and then 0%. 9.5% ammonia may be used for about 70% of the carbonitriding step a). The load bearing capacity of the steel component is increased by the carbonitriding step a). The load bearing capacity depends on the case depth reached by carbonitriding.

The steel component is then ferritically nitrocarburized (step b)), by re-heating the component to a temperature of 500-700 °C, preferably to a temperature below 590 °C in an atmosphere of 60% NH₃, 35% N₂ and 5% C0₂ for example. The ferritic nitrocarburizing step b) provides the steel component with a tough tempered core and a hard ceramic-like surface and a diffusion zone.

The steel component may subsequently be quenched (step c)) in an oil or salt bath with bath temperatures selected to achieve the optimum properties with acceptable levels of dimensional change. Hot oil/salt bath quenching can be used to minimize distortion of intricate parts. Low temperature tempering (step d)) may then be carried out to toughen the steel component, for example at a temperature of 150-260°C. After tempering, the component is cooled to room temperature and may then be used in any application in which it is likely to be subjected to stress, strain, impact and/or wear under a normal operational cycle, such as in under contaminated and/or poor lubricant conditions.

According to an embodiment of the invention the method may comprise the step of 5 tumbling the steel component after step b).

Such a method will improve at least one of the following properties of a steel component: wear resistance, corrosion resistance, load bearing capacity, surface hardness, core hardness, compound layer thickness, abrasive wear resistance, fatigue resistance.

10

Steel components subjected to a method according to an embodiment of the present invention may be used with or without subsequent grinding operations.

The steel component may comprise steel with a carbon content of 0.60 to 1.20 weight %, 15 100Cr6 steel, or a 100CrMo7 steel.

Such a method may be used to heat treat a steel component that comprises or constitutes a rolling element or roller, or a steel component for an application in which is subjected to alternating Hertzian stresses, particularly in applications with high demands 20 on wear and/or corrosion resistance.

Figure 2 shows a graph of Micro Vickers hardness profiles at 0.1 to 1 mm depth below the surface of a five steel materials 10, 12, 14, 16, 18 that were subjected to different heat treatments.

25

• Material 10 was 100Cr6 steel that had been through hardened and austenitically nitrocarburized.

• Material 12 was 100Cr6 steel that had been carbonitrided for 8 hours, re-hardened and austenitically nitrocarburized.

30 · Material 14 was 100Cr6 steel that had been carbonitrided for 8 hours, re-hardened and feritically nitrocarburized according to an embodiment of the present invention.

• Material 16 was 100Cr6 steel that had been carbonitrided for 8 hours and re- hardened.

• Material 18 was 100Cr6 steel that had been through hardened.

35 Samples of material 14 were ferritically nitrocarburized in a seal quench furnace at 580 °C for 2.5 hours in an atmosphere of 60% NH₃, 35% N₂ and 5% C0₂ Thereafter they were quenched in oil at 60 °C and tempered at 180 °C. Samples of material 10 and 12 were austenitically nitrocarburized under the same conditions as for the ferritic nitrocarburizing except that the temperature was raised to 620 °C. The main difference seen when increasing the process temperature from ferritic to austenitic nitrocarburizing was an increase in the compound layer thickness and the appearance of an austenite layer in between the compound layer and the substrate in austenitically nitrocarburized samples. The temperature for austenitic nitrocarburizing was selected to be high enough so that an austenite layer would be formed below the compound layer 33 but to be as low as possible to minimize distortions. Just before quenching, the samples were exposed to the atmosphere for a few seconds. This so called flash oxidation produced a thin oxide layer on the surface of the samples.

It can be seen from figure 2 that carbonitriding and ferritically nitrocarburizing a steel component in accordance with a method according to the present invention produces a steel component with a higher hardness in the diffusion zone than carbonitriding and austenitically nitrocarburizing a steel component. Carbonitriding prior to ferritic nitrocarburizing leads to a higher core and diffusion zone hardness than through hardening prior to ferritic nitrocarburizing.

Carbonitriding prior to nitrocarburizing increases both the diffusion zone and the core hardness, i.e. the hardness of the base material, compared to materials that are nitrocarburized in the soft condition, i.e. without carbonitriding prior to nitrocarburizing. However, the diffusion zone and core hardness is low compared to materials that are carbonitrided only.

Figure 3 shows the corrosion attack on both ferittically and austenitically nitrocarburized materials 20, 22, 24, 26, 28 and 30 after 104 in neutral salt spray.

• Material 20 was 100Cr6 steel that had been through hardened

• Material 22 was 100Cr6 steel that had been carbonitrided for 22 hours.

• Material 24 was 100Cr6 steel that had been carbonitrided for 8 hours and re- hardened. • Material 26 was 100Cr6 steel that had been carbonitrided for 22 hours and re- hardened.

• Material 28 was 50CrMo4 steel.

• Material 30 was C56E2 steel that had been carbonitrided for 8 hours and re- hardened.

Samples of all of the materials 20, 22, 24, 26, 28 and 30 were corrosion tested after they had been subjected to the heat treatments described above (see "reference" values in figure 3), and then after ferritic nitrocarburizing or austenitic nitrocarburizing. It can be seen from figure 3 that the samples subjected to heat treatments according to an embodiment of the invention (24, 26 and 28 when ferritically nitrocarburized) exhibited very good corrosion resistance.

Ferritic nitrocarburizing resulted in lowered corrosion attack compared to the reference for samples 24, 26 and 28. After 104 hours in neutral salt spray only 5-10% of the surface of the samples subjected to heat treatments according to an embodiment of the invention (24, 26 and 28 when ferritically nitrocarburized) was corroded.

Figure 4 is a micrograph showing 100Cr6 steel that had been carbonitrided for 8 hours, re-hardened and ferritically nitrocarburized in accordance with a method according to the present invention.

Figure 5 is a micrograph showing 100Cr6 steel that had been carbonitrided for 22 hours, re-hardened and ferritically nitrocarburized in accordance with a method according to the present invention.

The method according to the present invention produces a thin, hard case consisting of a ceramic iron-nitrocarbide layer (compound layer 33) and an underlying diffusion zone where nitrogen and carbon are dissolved in the matrix.

Steel components subjected to a method according to the present invention are, as a result of the method, provided with a compound layer 33 having a thickness of 10-20 μηη, a surface hardness of 800-1000 HV, which suggests a high resistance to abrasive wear, and a core hardness of 300-500 HV. Since the core is tough tempered, its crack propagation rate is low. Furthermore, it is believed that the compound layer 33 contains mostly ε-phase, which implies good resistance to adhesive wear.

Figure 6 shows an example of a steel component according to an embodiment of the invention, namely a rolling element bearing 34 that may range in size from 10 mm diameter to a few metres in diameter and have a load-carrying capacity from a few tens of grams to many thousands of tonnes. The bearing 34 according to the present invention may namely be of any size and have any load-carrying capacity. The bearing 34 has an inner ring 36 and an outer ring 38 and a set of rolling elements 40. The inner ring 36, the outer ring 38 and/or the rolling elements 40 of the rolling element bearing 34, and preferably at least part of the surface of all of the rolling contact parts of the rolling element bearing 40 may be subjected to a method according to the present invention.

Further modifications of the invention within the scope of the claims would be apparent to a skilled person.

Claims

1. Method for heat treating a steel component (34, 36, 38, 40), characterized in that said method comprises the steps of:

a) carbonitriding the steel component (34, 36, 38, 40), and

b) ferritically nitrocarburizing the steel component (34, 36, 38, 40).

2. Method according to claim 1 , characterized in that step b) is carried out at a temperature below 590 °C.

3. Method according to any of the preceding claims, characterized in that said steel component (34, 36, 38, 40) comprises steel with a carbon content of 0.60 to 1.20 weight %.

4. Method according to any of the preceding claims, characterized in that said steel component (34, 36, 38, 40) comprises a 100Cr6 steel or a 100CrMo7 steel.

5. Method according to any of the preceding claims, characterized in that said steel component (34, 36, 38, 40) comprises or constitutes a rolling element or roller, or a steel component for an application in which is subjected to alternating Hertzian stresses.

6. Method according to any of the preceding claims, characterized in that as a result of said method, said steel component (34, 36, 38, 40) is provided with a compound layer (33) having a thickness of 10-20 μπι.

7. Method according to any of the preceding claims, characterized in that as a result of said method, said steel component (34, 36, 38, 40) is provided with a surface hardness of 800-1000 HV and a core hardness of 300-500 HV.

8. Method according to any of the preceding claims, characterized in that step b) is carried out in an atmosphere of 60% NH₃, 35% N₂ and 5% C0₂.

9. Method according to any of the preceding claims, characterized in that step a) comprises carbonitriding the steel component (34, 36, 38, 40) for 5-25 hours.

10. Method according to any of the preceding claims, characterized in that it comprises the step of tumbling the steel component (34, 36, 38, 40) after step b).

11. Method according to any of the preceding claims, characterized in that it 5 comprises the steps of c) quenching the steel component (34, 36, 38, 40) and d) tempering the steel component (34, 36, 38, 40).

12. Method according to claim 10, characterized in that step d) is carried out at a temperature of 150-260 °C.

10

13. Method according to any of the preceding claims, characterized in that it is a method for improving at least one of the following properties of a steel component (34, 36, 38, 40): wear resistance, corrosion resistance, load bearing capacity, surface hardness, core hardness, compound layer thickness, abrasive wear resistance

15 14. , fatigue resistance.

15. Component (34, 36, 38, 40) made of steel, characterized in that said steel has a surface hardness of 800-1000 HV and a core hardness of 300-500 HV.

20 16. Steel component (34, 36, 38, 40) according to claim 14, characterized in that said steel comprises a compound layer having a thickness of 10-20 μΐη.

17. Steel component (34, 36, 38, 40) according to claim 14 or 15, characterized in that said steel has a carbon content of 0.60 to 1.20 weight %.

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18. Steel component (34, 36, 38, 40) according to any of claims 14-16, characterized in that said steel comprises a 100Cr6 steel or a 100CrMo7 steel.

19. Steel component (34, 36, 38, 40) according to any of claims 14-17, characterized 30 in that it comprises or constitutes a rolling element or roller, or a steel component (34, 36,

38, 40) for an application in which is subjected to alternating Hertzian stresses.

35