JP3094862B2 - Wear resistant sintered alloy bearing with low opponent aggression - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION The present invention has excellent conformability to a rotating shaft as a mating material and excellent self-lubricating properties, so that it has extremely low mating aggressiveness even in practical use under severe conditions. And a sintered alloy bearing exhibiting excellent wear resistance.

[0002]

2. Description of the Related Art Conventionally, in various driving devices, a sintered alloy bearing is generally used as a support member of a rotating shaft as a mating member. Indicates weight%), Cu: 10 to 30%, C:
It has a basic composition of 0.1 to 5%, with the balance being Fe and unavoidable impurities. Further, as shown in the microstructure enlarged view in FIG. It is well known that it is composed of a low-porosity Fe-Cu-C-based sintered alloy having a distributed structure and further having a porosity of 9% or less.

[0003]

On the other hand, in recent years, it has been remarkable that a drive device has been improved in performance, reduced in size, and further increased in output power. As a result, the rotation of a rotating shaft, which is a structural member of the drive device, has been accelerated. In addition, the load on the bearing tends to be high, but in the above-described conventional sintered alloy bearing, the low-pore Fe—Cu—C-based sintered alloy constituting the bearing is, as shown in FIG. Due to the hard pearlite phase, the compatibility with the rotating shaft, which is the mating material, is low, and the self-lubricating property is not sufficient.Therefore, at high speed rotation and high load conditions, the mating aggressiveness appears strongly and the wear progresses. It is unavoidable that it will be accelerated.

[0004]

Means for Solving the Problems Accordingly, the present inventors have
In view of the above, in order to develop a sintered alloy bearing having particularly excellent conformability and self-lubricating properties, the present inventors have conducted a study focusing on the above-mentioned conventional sintered alloy bearing, and have found that the above-mentioned conventional sintered alloy bearing Is contained in the low-porosity Fe-Cu-C-based sintered alloy, which contains S and boron nitride (hereinafter, referred to as BN), preferably hexagonal boron nitride (hereinafter, referred to as hBN) as alloy components. Since the S component serves as a nucleus to precipitate free graphite, and the BN component acts to promote the growth of the free graphite, the low-pore Fe—Cu—C sintered alloy is shown in FIG. As shown in the enlarged microstructure diagram, instead of the hard pearlite phase, a ferrite phase mainly composed of Fe is distributed via a Cu alloy bonding phase, and the S component is nucleated along the grain boundaries in the ferrite phase. Free graphite that has grown and dispersed In addition, a structure in which the BN component is distributed at the interface between the ferrite phase and the Cu alloy bonding phase is obtained. It has conformability and self-lubricating properties, and further has the low porosity Fe-Cu-C
Molybdenum sulfide system sintered alloy (hereinafter, indicated by MoS ₂₎
When BN is contained, BN is present at the interface between the ferrite phase and the Cu alloy bonding phase, as also shown in the enlarged microscopic view of FIG.
The self-lubricating properties are further improved by being distributed together with the components, so that when used under high-speed rotation and high-load conditions as a sintered alloy bearing, the opposing aggressiveness is extremely low, and excellent wear resistance is exhibited. That's the research result.

[0005] The present invention has been made based on the above-mentioned research results, and contains Cu: 10 to 30%,
C: 0.1-5%, S: 0.05-1%, BN:
0.1 to 3%, and if necessary, MoS
₂ : 0.5 to 2%, with the balance being Fe and unavoidable impurities, individual ferrite phases distributed via a Cu alloy bonding phase, and an S component as a nucleus in the ferrite phase. The grown free graphite is dispersed and distributed, and BN or BN is formed at the interface between the ferrite phase and the Cu alloy bonding phase.
And MoS ₂ distributed tissue and porosity of 9% or less,
The present invention is characterized by a wear-resistant sintered alloy bearing having a low aggressiveness formed by a low-pore Fe-Cu-C based sintered alloy having the following characteristics.

Next, the reason why the component composition and the porosity of the low porosity Fe—Cu—C based sintered alloy constituting the sintered alloy bearing of the present invention are limited as described above will be described. (A) Cu The Cu component has the effect of enabling liquid phase sintering and contributing to the improvement of sinterability and improving the strength.
If the content is less than 0%, the desired effect cannot be obtained, while if the content exceeds 30%, the abrasion resistance is reduced, so that the content is 10 to 30%, preferably 15%.
２５25%.

(B) C The C component has a function of precipitating as fine free graphite at crystal grain boundaries in the ferrite phase by the action of the S and BN components and growing to improve self-lubricating properties. If the proportion is less than 0.1%, the distribution ratio of free graphite is too small to secure the desired self-lubricating property, while if the proportion exceeds 5%, complete graphitization becomes difficult, and cementite is reduced. The ratio is set to 0.1 to 5%, and preferably to 1 to 3%, because the aggressiveness of the opponent increases due to precipitation.

(D) SS The S component is an indispensable component for the precipitation of free graphite as described above. Therefore, if its proportion is less than 0.05%, the graphitization becomes insufficient and the desired self-lubricating property is obtained. However, cementite precipitates to increase the aggressiveness of the opponent, and when the proportion exceeds 1%, the embrittlement is sharply reduced and the strength is reduced. ~
1%, preferably 0.1 to 0.7%.

(E) BN In the BN component, free graphite which is distributed at the interface between the ferrite phase and the Cu alloy bonding phase and precipitates at the grain boundaries in the ferrite phase with the S component as a nucleus grows, in other words, pearlite. It has the effect of graphitizing the cementite of the phase to convert the pearlite phase into a ferrite phase and free graphite, but if the ratio is less than 0.1%, the graphitization is insufficient, and the counterpart aggression due to the residual pearlite is inevitable. In addition, the desired self-lubricating property cannot be obtained. On the other hand, if the proportion exceeds 3%, the sinterability deteriorates and high strength cannot be secured, so that the proportion is 0.1 to 3%, desirably 0.1 to 3%. It was determined to be 0.5 to 2%.

(F) MoS _{2 The} MoS ₂ component is distributed as needed together with the BN component at the interface between the Cu alloy bonding phase and the ferrite phase to further improve self-lubricating properties. If the ratio is less than 0.5%, the desired effect cannot be obtained, while if the ratio exceeds 2%, the strength rapidly decreases. %, Preferably 0.5 to 1.5%.

(G) Porosity If the porosity exceeds 9%, the strength of the bearing is reduced, and it is not possible to cope with particularly when high strength is required. Therefore, the porosity is preferably 9% or less. Has been determined to be 7% or less.

[0012]

DESCRIPTION OF THE PREFERRED EMBODIMENTS Next, the sintered alloy bearing of the present invention will be specifically described with reference to examples. As a raw material powder, an atomized Fe—S alloy (S:
0.3%) powder, atomized Fe powder of -100 mesh, electrolytic Cu powder of -150 mesh, -1
A flake graphite powder of 00 mesh, a hBN powder of -100 mesh and a MoS ₂ powder of -100 mesh were prepared, and these raw powders were blended into the blending compositions shown in Tables 1 and 2 and lubricated. After adding 0.4% of zinc stearate as an agent and mixing with a V-type mixer for 30 minutes, the mixture was pressed into a green compact at a predetermined pressure in the range of 3.5 to 5 ton / cm ^2. The green compact is heated to a predetermined temperature in the range of 850 to 950 ° C. in an ammonia decomposition gas atmosphere for 30 minutes.
Sintered under the condition of holding for one minute, and made of a low-porosity Fe-Cu-C-based sintered alloy having a composition substantially the same as the porosity and the composition shown in Tables 1 and 2. Also, sintered alloy bearings 1 to 13 of the present invention and conventional sintered alloy bearings 1 to 5 having dimensions of outer diameter: 16 mm ^φ × inner diameter: 8 mm ^φ × length: 8 mm were manufactured, respectively. The sintered alloy bearings 1 to 13 of the present invention all have the structure shown in FIG. 1 or FIG. 2, and the conventional sintered alloy bearings 1 to 5 all have the structure shown in FIG. Was.

Next, each of the various sintered alloy bearings obtained as a result is vacuum-immersed in synthetic oil, as shown in FIG.
Is fitted into a support jig 1 of a radial friction tester shown in a schematic front view, and a rotary shaft 3 made of S45C (carbon steel) is
With a clearance of 25 μm, and a sintered alloy bearing 2, a support jig 1, and a ball bearing 4
The rotating shaft is rotated at a high speed of 10,000 rpm while a high load W of 20 kgf / cm ² is applied through
A wear test was performed for 00 hours of operation. After the test, the maximum wear depth of the sintered alloy bearing and the rotating shaft was measured. The measurement results are shown in Tables 1 and 2.

[0014]

[Table 1]

[0015]

[Table 2]

[0016]

According to the results shown in Tables 1 and 2, the sintered alloy bearings 1 to 13 of the present invention have a ferrite phase and this ferrite phase despite the severe conditions of high-speed rotation and high-load operation. Because it has excellent conformability and self-lubricating properties due to free graphite finely distributed in the inside,
While the wear of the rotating shaft as the mating material is small, that is, it shows excellent wear resistance with low mating aggressiveness, the conventional sintered alloy bearings 1 to 5 have the above-mentioned hard pearlite phase due to the hard pearlite phase. It is clear that under severe conditions, not only the opponent's aggressiveness is extremely high, but also the conformability is poor, so that uneven wear easily occurs. As described above, the sintered alloy bearing of the present invention has excellent conformability to the rotating shaft as a mating material and also has excellent self-lubricating properties, so that even under severe conditions, with extremely low mating aggressiveness, It exhibits excellent wear resistance over a long period of time.

[Brief description of the drawings]

FIG. 1 shows low-porosity Fe—C constituting a sintered alloy bearing of the present invention.
FIG. 3 is an enlarged schematic view of the structure of a u—C based sintered alloy.

FIG. 2 shows a low-porosity Fe—C constituting the sintered alloy bearing of the present invention.
FIG. 3 is an enlarged schematic view of the structure of a u—C based sintered alloy.

FIG. 3 shows a low-porosity Fe-Cu constituting a conventional sintered alloy bearing.
FIG. 3 is an enlarged schematic view of a structure of a C-based sintered alloy.

FIG. 4 is a schematic front view showing a radial type friction tester.

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 Supporting jig 2 Sintered alloy bearing 3 Rotating shaft 4 Ball bearing 5 Load cell

────────────────────────────────────────────────── ─── Continuation of the front page (56) References JP-A-9-49047 (JP, A) JP-A-9-49048 (JP, A) JP-A-9-49061 (JP, A) JP-A-9-490 49062 (JP, A) JP-A-9-49063 (JP, A) JP-A-9-49064 (JP, A) JP-A-9-41069 (JP, A) JP-A-9-41070 (JP, A) JP-A-9-41071 (JP, A) JP-A-56-169750 (JP, A) (58) Fields investigated (Int. Cl. ⁷ , DB name) C22C 33/02 C22C 38/00-38/60 B22F 5/00 F16C 33/10

Claims (2)

(57) [Claims] 1. Weight%, Cu: 10 to 30%, C: 0.1 to 5%, S: 0.05 to 1%, Boron nitride: 0.1 to 3
%, The balance being Fe and unavoidable impurities, the individual ferrite phases being distributed via the Cu alloy bonding phase,
Free graphite grown with the S component as a nucleus is dispersed and distributed in the ferrite phase.
Low pore Fe-Cu- having a structure in which boron nitride is distributed at the interface of the alloy bonding phase and a porosity of 9% or less.
A wear-resistant sintered alloy bearing having a low aggressiveness against a mating member, which is made of a C-based sintered alloy. 2. In weight%, Cu: 10 to 30%, C: 0.1 to 5%, S: 0.05 to 1%, Boron nitride: 0.1 to 3
% Of molybdenum sulfide: 0.5 to 2%, with the balance being Fe
And the composition of unavoidable impurities, the individual ferrite phases are distributed via the Cu alloy bonding phase,
And a structure in which free graphite grown with the S component as a nucleus is dispersed and distributed in the ferrite phase, and a structure in which boron nitride and molybdenum sulfide are distributed at an interface between the ferrite phase and the Cu alloy bonding phase; Porosity Fe-Cu-
A wear-resistant sintered alloy bearing having a low aggressiveness against a mating member, which is made of a C-based sintered alloy.