CN104561769A - Wear-resistant iron-based sintered metal - Google Patents
Wear-resistant iron-based sintered metal Download PDFInfo
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- CN104561769A CN104561769A CN201410527112.2A CN201410527112A CN104561769A CN 104561769 A CN104561769 A CN 104561769A CN 201410527112 A CN201410527112 A CN 201410527112A CN 104561769 A CN104561769 A CN 104561769A
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Abstract
The invention provides a wear-resistant iron-based sintered metal containing 0.02-2.0% of Mo and 0.2-1.2% of C according to mass percentage, the metal structure is formed by upper bainite, and the initial hardness is within the range of 120-400 HV.
Description
Technical field
The present invention relates to a kind of wearability iron-based sintering metal.
Background technology
Current, for the valve seat of oil engine using wearability iron-based sintering metal, require by combine with valve and keep the resistance to air loss of combustion chamber, and the wearability of requirement under the environment of high temperature drying is higher and to the aggressiveness of valve these characteristics lower.
In addition, in recent years, in order to response environment needs, raising engine output performance and low fuel consumption performance become indispensable measure, in the environment for use of valve seat, also, outside the condition requiring raising high temperature and high surface pressure, also require to improve the various condition such as thermal conductivity and low heat expansion property.
According to above-mentioned condition, such as there will be a known following oil engine valve seat, it contains Mo:0.4 ~ 4.0%, C:0.2 ~ 1.1%, Ni:0.6 ~ 5.0% by quality % ratio, the tissue that the mixed phase that metal structure presents only has bainite and martensite to mix is formed, and the ratio of the bainite and martensite at section place is 100:0 ~ 50:50, and substrate hardness is that 250 ~ 850HV(is such as with reference to Japanese Unexamined Patent Publication 2001-316780).
But hard powder is the powder that grit harder compared with the iron particle of iron-based powder is formed.Thus, by being dispersed in iron-base sintered alloy by grit, thus the wearability of iron-base sintered alloy can be improved.
The valve seat of above-mentioned iron-base sintered alloy in press-in cylinder head after, need in order to alignment adjustment etc. and machining carried out to the bearing surface abutted with valve, so also require high cutting.In other words, the longevity of the cutter that the valve seat of cutting excellence uses when contributing to machining is required.
But the valve seat of above-mentioned existing wearability iron-based sintering metal, owing to there is pore, is processed so become interrupted cut.Producing following problems thus, that is, is in the grit of more than 600HV containing lower bainite and martensitic initial hardness, and cutting is deteriorated, and shortens for the cutter life of processing.In addition, because the price of grit is very high, so produce materials cost this problem very high.
Summary of the invention
The present invention is only made up of the upper bainite that the carbide density not containing grit is higher, hardness can be suppressed at lower level.The invention provides a kind of wearability iron-based sintering metal of cheapness, can valve seat to be added to man-hour cutting excellent and cutter life can be suppressed to reduce, when being used as valve seat, significantly work hardening and there is stable wearability.
Wearability iron-based sintering metal involved in the present invention contains Mo:0.02 ~ 2.0%, C:0.2 ~ 1.2% by quality % ratio.The metal structure of wearability iron-based sintering metal is only made up of upper bainite, and the initial hardness of wearability iron-based sintering metal is in the scope of 120 ~ 400HV.
Because wearability iron-based sintering metal is only by not forming containing the upper bainite that the carbide density of grit is higher, thus hardness is suppressed at lower level, so can valve seat to be added to man-hour cutting excellent and cutter life can be suppressed to reduce.When wearability iron-based sintering metal is used as valve seat, significantly work hardening and there is stable wearability, and cheap.
Speed of cooling after sintering when wearability iron-based sintering metal is shaping also can be 40 ~ 150 DEG C/min.
Thereby, it is possible to formed, there is excellent cutting and the wearability iron-based sintering metal of wearability simultaneously.
The area occupation ratio of the carbide of wearability iron-based sintering metal also can be more than 40%.
According to this structure, can obtain that metal structure is only made up of upper bainite, there is excellent cutting and the wearability iron-based sintering metal of wearability simultaneously.
Wearability iron-based sintering metal also can by quality % than containing V:0.02 ~ 4.0%.
The average crystal particle diameter of wearability iron-based sintering metal also can be 2 ~ 40 μm.
Wearability iron-based sintering metal also can by quality % than containing Cr:0.05 ~ 2.0%.
In addition, wearability iron-based sintering metal also can by quality % than at least one contained in Ni:0.4 ~ 5.0%, Mn:0.05 ~ 1.0%.
According to the present invention, because wearability iron-based sintering metal is only made up of the upper bainite that the carbide density not containing grit is higher, thus hardness is suppressed at lower level, so can valve seat to be added to man-hour cutting excellent and cutter life can be suppressed to reduce.When wearability iron-based sintering metal is used as valve seat, significantly work hardening and there is stable wearability, and cheap.
Accompanying drawing explanation
Fig. 1 is the sectional view that wearability iron-based sintering metal involved by embodiments of the present invention is applied to the major portion of the cylinder head on valve seat.
Fig. 2 is the chart compared the wearing character of the perlite in the wearability iron-based sintering metal involved by embodiments of the present invention, upper bainite, lower bainite.
Fig. 3 be to the initial hardness of the upper bainite in the wearability iron-based sintering metal involved by embodiments of the present invention and lower bainite and sclerosis after the chart that compares of the characteristic of hardness.
Fig. 4 is the schematic diagram of the surface extruding sclerosis illustrated when the wearability iron-based sintering metal involved by embodiments of the present invention being applied to valve seat.
Fig. 5 is the chart compared the relation between the compressive residual stress of the upper bainite in the wearability iron-based sintering metal involved by embodiments of the present invention and lower bainite and case depth.
Fig. 6 is the explanatory view of the alternative photo in present condition of the upper bainite carbide under an optical microscope illustrated in the wearability iron-based sintering metal involved by embodiments of the present invention.
The speed of cooling of the upper bainite that Fig. 7 A ~ 7C represents in the wearability iron-based sintering metal involved by embodiments of the present invention is set to comparative example when 15 DEG C/min,
Fig. 7 A is the explanatory view of the alternative photo of the area occupation ratio of the carbide represented when proportioning is Fe-1.5Mo-0.5C,
Fig. 7 B is the explanatory view of the alternative photo of the area occupation ratio of the carbide represented when proportioning is Fe-1.5Mo-1.1C,
Fig. 7 C is the explanatory view of the alternative photo of the area occupation ratio of the carbide represented when proportioning is Fe-1.5Mo-2.0C.
Fig. 8 A ~ 8C represents the embodiment of the upper bainite in the wearability iron-based sintering metal involved by embodiments of the present invention, and comparative example when speed of cooling being set to 15 DEG C/min is shown,
Fig. 8 A is the explanatory view of the alternative photo of the area occupation ratio of the carbide represented when being Fe-1.5Mo-0.5C in proportioning and speed of cooling being set to 100 DEG C/min,
Fig. 8 B is the explanatory view of the alternative photo of the area occupation ratio of the carbide represented when being Fe-1.5Mo-1.1C in proportioning and speed of cooling being set to 60 DEG C/min,
Fig. 8 C is the explanatory view of the alternative photo of the area occupation ratio of the carbide represented when being Fe-1.5Mo-1.1C in proportioning and speed of cooling being set to 100 DEG C/min.
Fig. 9 is the figure of the relation between speed of cooling when being set to Fe-1.5Mo-1.1C of the proportioning of the upper bainite represented in the wearability iron-based sintering metal involved by embodiments of the present invention and abrasion loss.
Figure 10 is the explanatory view of the crystal grain of upper bainite in the wearability iron-based sintering metal involved by embodiments of the present invention.
Embodiment
Below, with reference to accompanying drawing, embodiments of the present invention are described.
As shown in Figure 1, the wearability iron-based sintering metal of present embodiment is applied to the valve seat 2 set by bottom surface side of the cylinder head 1 of engine (omission overall diagram).
Cylinder head 1 utilizes the part of its bottom surface to combustion chamber 3 to seal, and is formed with the exhaust channel 4 to combustion chamber 3 opening.The opening of combustion chamber 3 is by being arranged on vent valve 5 opening and closing on cylinder head 1.In addition, between the axle portion 5a and cylinder head 1 of vent valve 5, have valve guiding piece 6, its axle portion 5a supporting vent valve can move in the axial direction.
Vent valve 5 is utilizing valve body 5b that the opening of exhaust channel 4 is closed due to the drawing force of valve spring 7 at ordinary times.
Valve seat 2 embeds the bottom surface of cylinder head 1, and when exhaust channel 3 valve closing, the valve body 5b dropping place of vent valve 5 is on valve seat 2.
Valve seat 2 by by after shaping for the wearability iron-based sintering metal involved by present embodiment, carry out chamfering shape machining to the part of internal perisporium face for the dropping place part becoming vent valve 5 and forms.Form the wearability iron-based sintering metal of valve seat 2, by quality % than containing Mo:0.02 ~ 2.0%, C:0.2 ~ 1.2%, metal structure is only made up of upper bainite, and initial hardness is in the scope of 120 ~ 400HV.
Usually, bainite (bainite) is begun to cool down from austenitic state by carbon steel, the tissue produced when the temperature province between the temperature province of pearlitic transformation and the temperature (Ms point) starting martensitic transformation occurring and carrying out constant temperature maintenance.In the steel containing alloying elements such as Mo, not only in above-mentioned constant temperature keeps, produce bainite, under moderate speed, also produce bainite during continuous coo1ing.
Bainite is roughly divided into: with present during 450 ~ 550 DEG C of degree process of constant temperature treatment temp close to the upper bainite of pearlitic black plumage shape tissue and to process at lower than the temperature closer to Ms point of aforementioned temperature time present lower bainite close to martensitic acicular structure.
Upper bainite as shown in Figure 2, has the tissue characteristics that abrasion loss is lower compared with perlite and lower bainite.In addition, upper bainite as shown in Figure 3, has the hardness of initial hardness lower than lower bainite and after sclerosis higher than the tissue characteristics of lower bainite.
Thus, upper bainite can easily carry out, on the basis of machining etc., to its process tool processed not easy damaged, can contributing to tool bit life under initial hardness.In addition, abrasion loss is less after curing for upper bainite.Thus, such as, shown in Fig. 4, when being made by vent valve 5 exhaust channel 4 become valve closing state from valve opening state, utilizing the surface pressure of valve body 5b dropping place in valve seat 2 and organizing (plasticity) to harden.Meanwhile, the surfaceness of valve seat 2 reduces (density raising) and guarantees wearability, and valve seat 2 can be suppressed to wear and tear.That is, the roughness due to surface is different, and wearing character significantly changes.
, obtain new discovery here, that is, under the environment for use of valve seat 2, upper bainite compared with other tissue, work hardening amount and hardening depth higher, excellent in wear resistance.
Specifically, as shown in Figure 5, compressive residual stress (MPa) along with case depth (μm) darker, more unfavorable to fatigue strength.And upper bainite, compared with lower bainite, obtains following result, that is, on the basis favourable for fatigue strength, the change relative with case depth is less.
Therefore, consider the characteristic of above-mentioned upper bainite, in the present embodiment, valve seat 2 is made up of following wearability iron-based sintering metal, namely, this wearability iron-based sintering metal only by by quality % than being inevitable impurity and Fe containing Mo:0.02 ~ 2.0%, C:0.2 ~ 1.2%, remainder, its metal structure is only made up of upper bainite.
That is, Mo can make excellent in wear resistance, and can improve hardenability.Now, if the mass ratio of Mo is lower than 0.02%, be then difficult to fully obtain above-mentioned effect, if more than 2.0%, then material powder is hardening, formability deteriorates.
In addition, C can improve wearability while formation carbide.If the mass ratio of C is lower than 0.2%, then hardness is not enough, if more than 1.2%, then cause increasing the aggressiveness of other parts owing to generating proeutectoid cementite, cutting also worsens.
In the present embodiment, make the reason of initial hardness in the scope of 120 ~ 400HV of wearability iron-based sintering metal as follows.If initial hardness is less than 120HV, then hardness during work hardening cannot arrive 600HV, and wearability is not enough.In addition, if initial hardness is more than 400HV, hardness then during work hardening is excessive, generation makes wearing and tearing valve seat being carried out to the cutter of machining increase to the aggressiveness of other parts, and machining becomes difficulty, in addition, when being used as valve seat, although wearability is enough large, the aggressiveness for valve becomes large.
In the present embodiment, the speed of cooling after sintering during by making shaping in the scope of 40 ~ 150 DEG C/min, thus makes in image analysis, and in the visual field of 0.19 × 0.23MM, the area occupation ratio of carbide is more than 40%.In addition, as shown in Figure 6, in the in-built situation of observing crystal grain with opticmicroscope (× 1000), illustrated black part is divided into carbide.
In addition, the situation of the image shown in Fig. 6 be by Fe-1.5Mo alloy powder, C, lubricant by quality % than the forming materials mixed together in the mode of 98:1:1 and under the nitrogen environment of 1120 DEG C after sintering, situation about obtaining with 100 DEG C of coolings.
Here, the composition of lubricant refers to, makes the rear de-lubricant operation of discharging of this lubricant gasification by having in sintering process, thus the composition that sintered compact does not after shaping remain.Thus, when utilizing Fe-1.5Mo-1.1C to make the sintered compact of 100g, be carry out powder mixing with the ratio of 98:1.2:0.8 strictly speaking.Therefore, become 1.1C by normally removing the graphite of 0.1, and become 98:1.1:0 by discharging lubricant, its result becomes Fe-1.48Mo-1.1C.
Fig. 7 A ~ 7C illustrates with shaping: 8.0 ton/Cm
2, sintering: when the condition of 1120 DEG C × 60min and speed of cooling are set to 15 DEG C/min, the area occupation ratio of carbide is the example of less than 40% in image analysis in the visual field of 0.19 × 0.23MM.
In fig. 7, when with the proportioning of Fe-1.5Mo-0.5C and speed of cooling is set to 15 DEG C/min, apparent hardness is 150HV, but the area occupation ratio of carbide is about 30%, becomes the sintered compact that wearability is poor.
In figure 7b, when with the proportioning of Fe-1.5Mo-1.1C and speed of cooling is set to 15 DEG C/min, apparent hardness is 168HV, and the area occupation ratio of carbide is about 35%, becomes the sintered compact that wearability is poor.
In fig. 7 c, when with the proportioning of Fe-1.5Mo-2.0C and speed of cooling is set to 15 DEG C/min, apparent hardness is 169HV, but the area occupation ratio of carbide is about 38%, becomes the sintered compact that wearability is poor.
As implied above, even if the proportioning of known C in mass ratio improves, as long as but speed of cooling is lower, then and the area occupation ratio of the carbide of sintered compact is lower compared with apparent hardness, is difficult to guarantee wearability.
On the other hand, Fig. 8 A ~ 8C illustrates with shaping: 8.0 ton/Cm
2, sintering: when the condition of 1120 DEG C × 60min and speed of cooling are set to 60 ~ 100 DEG C/min, the area occupation ratio of carbide is the example of more than 40% in image analysis in the visual field of 0.19 × 0.23MM.
In fig. 8 a, ground identical with Fig. 7 A proportioning is Fe-1.5Mo-0.5C, speed of cooling is set to 100 DEG C/min.In the case, apparent hardness is higher 190HV, and the area occupation ratio of carbide also ensures about 42%, becomes the sintered compact that wearability is higher.In addition, in fig. 8 a, such as illustrating black part near the upper left corner due to emptying aperture causes.
In the fig. 8b, ground identical with Fig. 7 B proportioning is Fe-1.5Mo-1.1C, speed of cooling is set to 60 DEG C/min.In the case, apparent hardness is 209HV, and the area occupation ratio of carbide is about 60%, becomes the sintered compact that wearability is higher.
In Fig. 8 C, ground identical with Fig. 7 B proportioning is Fe-1.5Mo-1.1C, speed of cooling is set to 100 DEG C/min.In the case, apparent hardness is 210HV, does not have difference compared with the situation of speed of cooling 60 DEG C/min, but the area occupation ratio of carbide becomes about 72% tremendously, becomes the sintered compact that wearability is higher.
As mentioned above, even if the proportioning of known C in mass ratio improves, as long as but speed of cooling is lower, then and the area occupation ratio of the carbide of sintered compact is lower compared with apparent hardness, is difficult to guarantee wearability.
In addition, as shown in Figure 9, with identical with Fig. 8 B, 8C ground proportioning for Fe-1.5Mo-1.1C, speed of cooling is confirmed in the scope of about 10 ~ 100 DEG C/min.Its result, if confirm speed of cooling more than 40 DEG C/min, then becomes the sintered compact more excellently can guaranteeing apparent hardness and wearability.
Thus, when by the upper bainite that Fe-1.5Mo-1.1C is formed, for speed of cooling, there is pearlitic transformation if known lower than 50 DEG C/min, if more than 150 DEG C/min, start martensitic transformation.
As implied above, if the speed of cooling after sintering time shaping is set to 40 ~ 150 DEG C/min, then the area occupation ratio of carbide can be ensured more than 40%, the wearability iron-based sintering metal simultaneously realizing wearability and cutting can be realized.
In addition, although the wearability of the more sparse upper bainite of the precipitation state of known carbide is lower, the wearability of the upper bainite that the precipitation state of carbide is closeer is higher, and the tissue of the intensive upper bainite to the limit of carbide becomes the tissue of lower bainite.Thus, even if the precipitation state of known carbide is overstocked, it is poor also to become work hardening, and wearability reduces.
As implied above, in existing valve seat, with the addition of the grit that stone price is very high in order to ensure wearability, materials cost uprises and cutter life shortens.
On the other hand, the valve seat 2 of present embodiment can maintain following condition:
(1) for preventing the airtight maintenance function of pressurized gas or combustion gas leakage
(2) the heat conduction function for making the heat of vent valve 5 overflow to cylinder head 1 side
(3) intensity of the impact when the valve body 5b dropping place of vent valve 5 can be born
(4) aggressiveness to vent valve 5 is reduced
While, guarantee following condition:
(5) nonabradable wear-resistant function at Gao Re and under the environment of high capacity
(6) reasonable price
(7) add be easy to man-hour cut.
As implied above, in the present embodiment, not containing grit, upper bainite hardens due to the surface pressure of vent valve 5 in actual machine (engine), easily can play wearability, and, the hardness adding man-hour is lower, and without the need to sacrificing cutter life, cutting is excellent.
In addition, in the above-described embodiment, show the example containing Mo:0.02 ~ 2.0%, C:0.2 ~ 1.2%, but also such as can contain Cr:0.05 ~ 2.0% or V:0.02 ~ 4% by quality % ratio.That is, can be formed as Mo-C-Cr, any one of Mo-C-V, Mo-C-Cr-V distributes.
Cr has makes the perlitic range of CCT line chart move to the side that speed of cooling is slower, and the effect that bainite range is expanded, if lower than 0.05%, effect is insufficient, if more than 2.0%, easily occurs the martensite of hard, and cutting is deteriorated.
V has the effect making crystal grain granular, if lower than 0.02%, effect is insufficient, if more than 4.0%, forms V carbide in a large number, uprises the aggressiveness of other parts.
Specifically, in the present embodiment, be rendered as upper bainite for condition with metal structure entirety, by containing V:0.02 ~ 4%, thus the average crystal particle diameter of upper bainite can be made to become 2 ~ 40 μm.If speed of cooling is too fast, then when average crystal particle diameter is less than 2 μm, is difficult to present the metal structure only with upper bainite, includes, to other parts, there is aggressive martensite.In addition, if speed of cooling is excessively slow, then average crystal particle diameter is greater than 40 μm, and pearlitic transformation occurs.Metal structure entirety is rendered as the condition of upper bainite and speed of cooling described later is closely related.
In addition, average crystal particle diameter is each lattice in the left side of Figure 10 is the situation of crystal grain.Here, the internal structure of crystal grain is as shown in the right side of Figure 10, and in SEM photo (× 4000), illustrated white portion is carbide.That is, should observe white portion exactly as shown in the right side of Figure 10 is carbide, and carbide is not etched so become white, and the substrate of the periphery of carbide then becomes black.On the other hand, when being observed by opticmicroscope, cannot observe so far, as shown in Figure 6, can by diagram black part as the part that there is carbide.
In addition, in the present embodiment, also can by quality % than at least one contained in Ni:0.4 ~ 5.0%, Mn:0.05 ~ 1.0%.That is, any one combination of Mo-C-Ni, Mo-C-Mn, Mo-C-Ni-Mn can also be had.In addition, one of them kind (being such as Mo-C-Cr-Ni) of above-mentioned Cr:0.05 ~ 2.0%, V:0.02 ~ 4% can still be contained.
Can improve the character of the mechanical aspects of wearability iron-based sintering metal further containing Ni and Mn, be useful.
Ni mainly considers that thermotolerance erosion resistance is added, if be less than 0.4%, then effect is insufficient, if more than 5.0% also effect cannot improve further, and easily to wear and tear.
Mn mainly considers that erosion resistance is added, if be less than 0.05%, effect is insufficient, if also cannot effect cannot improve further more than 1.0%, and reduces wearability and intensity.
In addition, in the above-described embodiment, the valve seat 2 of the exhaust side being configured in engine is illustrated, but is configured in air inlet side and also can realizes identical effect.
In addition, in present embodiment, valve seat 2 is applied to for by wearability iron-based sintering metal, the surface pressure applied by vent valve 5 makes the situation of the hardening of tissue be illustrated, but also can be applied to wearability iron-based sintering metal is used as such as realized case-hardened various parts by shot peening technology, situation that the various parts that use grinding tool to be formed by the cold forging of compressed moulding and the various parts etc. that implement dimensioned or rolling processing aftershaping in order to correct shape need the metallic substance of viscous deformation.
As described above, wearability iron-based sintering metal involved in the present invention is only made up of the upper bainite that the carbide density not containing grit is higher, thus there is following effect, namely, hardness is suppressed at lower level, so can valve seat to be added to man-hour cutting excellent and cutter life can be suppressed to reduce.When wearability iron-based sintering metal is used as valve seat, there is following effect, that is, through significantly work hardening, there is stable wearability, and cheap.Especially, under the environment being applied to high temperature or high surface pressure, need the wearability iron-based sintering metal of the parts of initial manufacture etc. all effective.
Claims (7)
1. a wearability iron-based sintering metal, is characterized in that,
By quality % than containing Mo:0.02 ~ 2.0% and C:0.2 ~ 1.2%, metal structure is only made up of upper bainite, and initial hardness is in the scope of 120 ~ 400HV.
2. wearability iron-based sintering metal according to claim 1, is characterized in that,
Speed of cooling after sintering time shaping is 40 ~ 150 DEG C/min.
3. wearability iron-based sintering metal according to claim 1 and 2, is characterized in that,
The area occupation ratio of carbide is more than 40%.
4. wearability iron-based sintering metal according to any one of claim 1 to 3, is characterized in that,
By quality % than containing V:0.02 ~ 4.0%.
5. wearability iron-based sintering metal according to claim 4, is characterized in that,
Average crystal particle diameter is 2 ~ 40 μm.
6. wearability iron-based sintering metal according to any one of claim 1 to 5, is characterized in that,
By quality % than containing Cr:0.05 ~ 2.0%.
7. wearability iron-based sintering metal according to any one of claim 1 to 6, is characterized in that,
By quality % than at least one contained in Ni:0.4 ~ 5.0%, Mn:0.05 ~ 1.0%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
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| JP2013-213338 | 2013-10-11 | ||
| JP2013213338A JP5910600B2 (en) | 2013-10-11 | 2013-10-11 | Wear-resistant iron-based sintered metal |
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| CN104561769A true CN104561769A (en) | 2015-04-29 |
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| EP0711845A1 (en) * | 1994-11-09 | 1996-05-15 | Sumitomo Electric Industries, Ltd. | Wear-resistant sintered ferrous alloy for valve seat |
| JPH08333659A (en) * | 1995-06-06 | 1996-12-17 | Mitsubishi Materials Corp | Ferrous sintered alloy excellent in strength and wear resistance |
| US5834664A (en) * | 1996-01-19 | 1998-11-10 | Hitachi Powdered Metals Co., Ltd. | Wear-resistant sintered alloy, and its production method |
| US20010037842A1 (en) * | 2000-02-05 | 2001-11-08 | Koichiro Hayashi | Valve seat for internal combustion engines |
| JP2002322503A (en) * | 2001-04-24 | 2002-11-08 | Toyota Motor Corp | Method for producing sintered steel parts |
| CN1837397A (en) * | 2005-03-23 | 2006-09-27 | 日本活塞环株式会社 | Iron-base sintered alloy valve holder materials for internal combustion engine |
| US20100310405A1 (en) * | 2009-06-05 | 2010-12-09 | Toyota Jidosha Kabushiki Kaisha | Ferrous sintered alloy, process for producing ferrous sintered alloy and connecting rod |
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2013
- 2013-10-11 JP JP2013213338A patent/JP5910600B2/en not_active Expired - Fee Related
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2014
- 2014-10-09 CN CN201410527112.2A patent/CN104561769A/en active Pending
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| JPS61183444A (en) * | 1985-02-08 | 1986-08-16 | Toyota Motor Corp | High strength sintered alloy and its manufacture |
| JPS6462442A (en) * | 1987-08-31 | 1989-03-08 | Teikoku Piston Ring Co Ltd | Ferrous sintered alloy for valve seat |
| JPH05140701A (en) * | 1991-11-15 | 1993-06-08 | Mitsubishi Materials Corp | Two layer valve seat made of ferrous sintered alloy for internal combustion engine |
| EP0711845A1 (en) * | 1994-11-09 | 1996-05-15 | Sumitomo Electric Industries, Ltd. | Wear-resistant sintered ferrous alloy for valve seat |
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| US20100310405A1 (en) * | 2009-06-05 | 2010-12-09 | Toyota Jidosha Kabushiki Kaisha | Ferrous sintered alloy, process for producing ferrous sintered alloy and connecting rod |
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| Publication number | Publication date |
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| JP2015074819A (en) | 2015-04-20 |
| JP5910600B2 (en) | 2016-04-27 |
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Application publication date: 20150429 |