Technical field
[0001] The present invention relates to an improved vanadium alloyed bearing steel.
Background
[0002] The hardness after martensitic hardening of a soft annealed bearing steel, e.g. AISE
52100 is highly dependent on the carbon content in solid solution and thus the austenitisation
conditions for a given quench. A higher austenitisation temperature or longer time
leads to more dissolution of carbides. The optimum carbon content in solid solution
to give the highest hardness is considered to be somewhere between 0.6 to 0.8 weight%
for an oil quenched component. A lower carbon content will give a softer martensite.
A higher carbon content will lead to an increased retained austenite content which
would decrease the hardness and give a disadvantageous martensite morphology. Furthermore,
a too large amount of retained austenite will give poor structural stability.
[0003] Hardened bearing steels are often subjected to wear. To improve wear properties it
is necessary to maximize the hardness. However, this could also be further improved
by introducing a fraction of hard carbides such as VC.
[0004] The toughness of a component made from a bearing steel is relatively low. This could
result in catastrophically failure and it would therefore be appreciated to increase
the toughness. This could be achieved by alloying with Ni which is an element that
improves the toughness.
[0005] Structural stability is important for critical applications and could be improved
by Si alloying. Si retards the precipitation of carbide during tempering and thus
improves the stability. This could also be beneficial for reducing tempering embrittlement
since the precipitation of grain boundary carbides could be reduced.
[0006] Large components require a high hardenability to enable thorough hardening. The hardenability
could be increased with alloying additions.
The Invention
[0007] The object of the invention is to provide a steel designed to exhibit greater tolerances
in austenitising temperature and time to give optimum carbon content.
[0008] This is achieved with the steel according to the present invention, having the following
analysis, in weight-%:
| C |
0.60 - 1.10 |
| Si |
0 - 2.10 |
| Mn |
0 - 2.00 |
| Ni |
0 - 2.00 |
| Cr |
0 - 2.00 |
| Mo |
0 - 0.75 |
| V |
0.25 - 1.00 |
| Fe |
incl. possible impurities - ad. 100%. |
[0009] By alloying with carbide formers, preferably V and also Cr, compared to standard
bearing steels, an optimal carbon content is obtained. A higher wear resistance is
obtained because of the presence hard VC carbides. Improved toughness can be obtained
by Ni addition and a high structural stability can be obtained with Si additions.
The required hardenability is balanced by adding Cr, Mo and Mn.
[0010] According to one embodiment of the invention the steel has the following analysis,
in weight-%:
| C |
0.60 - 1.00 |
| Si |
0.40 - 2.10 |
| Mn |
0.10 - 1.00 |
| Ni |
0.50 - 2.00 |
| Cr |
0 - 2.00 |
| Mo |
0 - 0.50 |
| V |
0.25 - 1.00 |
| Fe |
incl. possible impurities - ad. 100%. |
[0011] According to another embodiment of the invention the steel has the following analysis,
in weight-%:
| C |
0.75 - 0.95 |
| Si |
0.80 - 1.80 |
| Mn |
0.10 - 1.00 |
| Ni |
0.50 - 1.50 |
| Cr |
0 - 2.00 |
| Mo |
0 - 0.50 |
| V |
0.40 - 0.80 |
| Fe |
incl. possible impurities - ad. 100%. |
Brief description of the Drawings
[0012] The invention will be described more in detail below with reference to the accompanying
drawings, in which
Fig. 1 shows mole-% of phases in equilibrium versus temperature for steel A,
Fig. 2 shows a graph corresponding to Fig. 1, for a steel B,
Fig. 3 shows the carbon content in the austenite versus temperature for the steel
A, and
Fig. 4 shows a graph corresponding to Fig. 3 for the steel B.
Description of preferred embodiments
[0013] The steel should have sufficient vanadium content to form vanadium carbides which
stops excessive carbon from going into solid solution at the austenitisation temperature
range. The carbon content and vanadium content should be balanced so that the equilibrium
carbon content is optimal at the chosen austenitisation temperature. Such a composition
is shown in Table 1.
Table 1
| Vanadium alloyed bearing steel according to the invention |
| |
C |
Si |
Mn |
Cr |
Ni |
Mo |
V |
| min |
0.60 |
0 |
0 |
0 |
0 |
0 |
0.25 |
| max |
1.10 |
2.10 |
2.00 |
2.00 |
2.00 |
0.75 |
1.00 |
| Example |
0.85 |
1.30 |
0.30 |
1.40 |
1.00 |
- |
0.60 |
[0014] A theoretical calculation using the thermodynamic simulation program Thermocalc shows
the effect of a vanadium addition. The addition will lead to the formation of a carbide
that is stable at higher temperatures. Two steels are compared; steel A with a vanadium
addition and steel B without vanadium. The compositions are shown in Table 2.
Table 2
| Chemical composition in weight-%. |
| Steel |
C |
Si |
Mn |
Cr |
Ni |
Mo |
V |
| A |
0,85 |
1,30 |
0,30 |
1,40 |
1,00 |
- |
0,60 |
| B |
0,85 |
1,30 |
0,30 |
1,40 |
1,00 |
- |
- |
[0015] In Fig. 1 a graph illustrating the mole percentage of phases in equilibrium versus
temperature is shown for a steel according to Table 2. For this vanadium steel a carbide
(VC) is stable up to approximately 1200°C. In Fig. 2, the corresponding graph illustrates
that steel B does not have this fraction of carbides.
[0016] The fact that vanadium forms carbides which are stable at a higher temperature results
in a wider temperature range for dissolving carbides and thus saturating the austenitic
matrix with carbon. This is schematically shown in Figs. 3 and 4, wherein the equilibrium
carbon content in austenite (the rest of the carbon is bonded in carbides) is plotted
versus temperature. For steel A, Fig. 3, the maximum carbon content (equilibrium)
in austenite for a austenitisation temperature of 830-900°C is 0.72 to 0.74 weight-%.
For steel B, Fig. 4, the same temperature range gives a carbon content of between
0.75 and 0.85 weight-%. This means that for steel B the time at austenitisation temperature
is much more critical for the carbon content obtained. Furthermore, steel B will not
have the fraction of hard vanadium carbides which is beneficial for the wear properties.
