CN1833799A - Iron sintered component and producing method and sintered mechanical parts - Google Patents
Iron sintered component and producing method and sintered mechanical parts Download PDFInfo
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- CN1833799A CN1833799A CN 200610067694 CN200610067694A CN1833799A CN 1833799 A CN1833799 A CN 1833799A CN 200610067694 CN200610067694 CN 200610067694 CN 200610067694 A CN200610067694 A CN 200610067694A CN 1833799 A CN1833799 A CN 1833799A
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 149
- 229910052742 iron Inorganic materials 0.000 title claims abstract description 68
- 238000000034 method Methods 0.000 title claims description 31
- 239000000843 powder Substances 0.000 claims abstract description 99
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 65
- 239000000463 material Substances 0.000 claims abstract description 46
- 238000005245 sintering Methods 0.000 claims abstract description 45
- 239000010949 copper Substances 0.000 claims abstract description 43
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 41
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 33
- 229910052802 copper Inorganic materials 0.000 claims abstract description 32
- 238000004519 manufacturing process Methods 0.000 claims abstract description 29
- JKWMSGQKBLHBQQ-UHFFFAOYSA-N diboron trioxide Chemical compound O=BOB=O JKWMSGQKBLHBQQ-UHFFFAOYSA-N 0.000 claims abstract description 28
- 229910000881 Cu alloy Inorganic materials 0.000 claims abstract description 17
- 239000000203 mixture Substances 0.000 claims abstract description 17
- 230000008595 infiltration Effects 0.000 claims description 61
- 238000001764 infiltration Methods 0.000 claims description 61
- 229910052810 boron oxide Inorganic materials 0.000 claims description 27
- 238000009792 diffusion process Methods 0.000 claims description 26
- 229910002804 graphite Inorganic materials 0.000 claims description 25
- 239000010439 graphite Substances 0.000 claims description 25
- 229910052796 boron Inorganic materials 0.000 claims description 8
- 229910052751 metal Inorganic materials 0.000 claims description 8
- 239000002184 metal Substances 0.000 claims description 8
- 238000007493 shaping process Methods 0.000 claims description 8
- 239000000428 dust Substances 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 5
- 238000002156 mixing Methods 0.000 claims description 2
- 229910001562 pearlite Inorganic materials 0.000 abstract description 14
- 238000005520 cutting process Methods 0.000 abstract description 2
- 238000010438 heat treatment Methods 0.000 abstract description 2
- 229910011255 B2O3 Inorganic materials 0.000 abstract 1
- 238000000465 moulding Methods 0.000 abstract 1
- 239000011159 matrix material Substances 0.000 description 44
- 239000011812 mixed powder Substances 0.000 description 14
- 230000000694 effects Effects 0.000 description 12
- 238000005516 engineering process Methods 0.000 description 10
- 229910000859 α-Fe Inorganic materials 0.000 description 10
- 239000011148 porous material Substances 0.000 description 8
- 150000001639 boron compounds Chemical class 0.000 description 7
- 229910052582 BN Inorganic materials 0.000 description 5
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 5
- 238000012797 qualification Methods 0.000 description 5
- 239000007791 liquid phase Substances 0.000 description 4
- 238000003754 machining Methods 0.000 description 4
- 239000003973 paint Substances 0.000 description 4
- 239000011248 coating agent Substances 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 229910002090 carbon oxide Inorganic materials 0.000 description 2
- 230000004927 fusion Effects 0.000 description 2
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 238000005457 optimization Methods 0.000 description 2
- 235000011837 pasties Nutrition 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 239000004576 sand Substances 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 239000000796 flavoring agent Substances 0.000 description 1
- 235000019634 flavors Nutrition 0.000 description 1
- 238000005470 impregnation Methods 0.000 description 1
- 150000002505 iron Chemical class 0.000 description 1
- MOWNZPNSYMGTMD-UHFFFAOYSA-N oxidoboron Chemical group O=[B] MOWNZPNSYMGTMD-UHFFFAOYSA-N 0.000 description 1
- 238000007591 painting process Methods 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000008961 swelling Effects 0.000 description 1
- 230000001988 toxicity Effects 0.000 description 1
- 231100000419 toxicity Toxicity 0.000 description 1
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Abstract
The invention relates to an iron sinter element and relative production, which can improve high strength and cutting property. Wherein, arranging the fuse dip material formed by molding metallic powder on at least one part of the surface of sinter element that obtained by heating the powder former on the iron sinter element; sintering the powder former with said fuse dip material, at the temperature above the carbon disperse temperature and under the fuse point of fuse dip material; and said powder is the iron powder mixture that removed graphite powder from the power mixture of iron sinter element that in pearlite organism; adding 0.01-1.0 mass% boric oxide and 0.1-2.0 mass% graphite powder, then said metallic powder is the copper or copper alloy powder.
Description
Technical field
The present invention relates to iron and be the manufacture method of sintered component and utilizing its iron that obtains is sintered component and sintered mechanical part, and particularly relating in a sintered component iron of can be respectively setting the position of the position of good strength and excellent in machinability with high standard is the manufacturing technology of sintered component.
Background technology
Mechanical properties such as the iron that utilizes the powder metallurgic method manufacturing is that sintered component is cheap for manufacturing cost, intensity and abrasion performance are good, therefore are used in various fields.This iron be sintered component when being used for mechanical part etc., need machining behind the sintering sometimes, at this moment need good especially machinability.
Therefore, consider this point,, proposed all technology in order to improve the machinability that iron is sintered component.Promptly, No. 3325173 communique of Japan special permission the surface coating of formed body, presintering body and sintered body at the ferrous material of the carbon containing that utilizes powder metallurgic method to make is disclosed and in pore the solution of impregnation boracic, afterwards sintering and again the iron of sintering be the method for modifying of agglomerated material.In addition, Japan's No. 3410326 communique of special permission discloses a kind of manufacture method of steelmet, this method possesses: on the surface of the presintering body that the steelmet of heating carbon containing under the temperature below the diffusion temperature of carbon obtains with the powder compact of powder or this powder compact, be coated with the operation of the pasty state top paint of boron-containing compound; Be coated with the operation of the above-mentioned powder compact or the presintering body of above-mentioned top paint with the sintering temperature more than the diffusion temperature of carbon.
No. 3413628 communique of Japan special permission discloses also that a kind of to be used to obtain iron be that the iron of agglomerated material is mixture of powders, described iron is that agglomerated material is to be that the iron of having removed powdered graphite the mixture of powders used of agglomerated material is mixture of powders with respect to the iron that presents pearlitic structrure behind sintering, adding match ratio is the boron oxide of 0.01～1.0 quality % and the powdered graphite of 0.1～2.0 quality %, and presents the tissue that has disperseed graphite behind the sintering in the matrix that is made of ferrite and pearlite.In addition, TOHKEMY 2000-144350 communique also discloses a kind of free-cutting machinability steelmet that is dispersed with free graphite in matrix, its matrix hardness is 150～250HV, and all composition by quality ratio, be P:0.1～1.0%, B:0.003～0.31%, O:0.007～0.69%, C:0.1～2.0%, surplus is Fe and unavoidable impurities.
But, the technology of above-mentioned No. 3325173 communique of Japan's special permission and No. 3410326 communique record of Japan's special permission, it is the diffusion of the carbon when utilizing the boron compound of applied grade on assigned position to suppress sintering powder compact etc., suppress the generation of matrix medium pearlite, generate the good tissue that constitutes by ferrite and pearlite of machinability.Though this technology can improve the machinability of necessary position, need be before presintering or before the sintering on formed body etc. the operation of coating boron compound and the operation of coating pasty state top paint., need require efforts before sintering for this reason, need the equipment that uses in the painting process of top paint simultaneously, making has problem economically.
In addition, the technology of above-mentioned No. 3413628 communique of Japan's special permission and the record of TOHKEMY 2000-144350 communique, by making the composition optimization of material powder, utilize boron oxide to suppress the diffusion of carbon to matrix, obtain the good tissue that constitutes by ferrite and pearlite of machinability.This technology only can improve the machinability of sintered component easily by the selected material powder, but the intensity of the position that does not need machinability of sintered component reduces.For this reason, when being applied to mechanical part, can't give intensity and machinability respectively, the leeway of improvement is still arranged.
In recent years,, not only require to realize intensity and machinability, also require in a sintered component, only to give these characteristics each necessary position with high standard particularly along with the high performance of automobile component etc.For example, requirement is possessing the sintered mechanical part that is used for by the bolt hole of bolted banding, intensity by the part that will contact with the bolt supporting surface becomes higher, can fully tolerate the stress that produces on the above-mentioned contact portion, and become higher by machinability with other parts, can implement machining efficiently.
The present invention forms in view of above present situation, it is the manufacture method of sintered component and to utilize its iron that obtains be sintered component and sintered mechanical part that its purpose is to provide iron, described iron is that sintered component not only can high standard realize intensity and machinability, also can only give these characteristics to each necessary position.
Summary of the invention
The inventor is in view of the demand, is that the manufacturing technology of sintered component has carried out inquiring into keen determination for the iron that can only give each necessary position intensity and machinability with high standards.In the prior art, as mentioned above, when manufacturing iron is sintered component, as material powder, when preparing iron powder and carbon dust, add the boron compound of solution state or pulverulence, carry out sintering, thus, as the tissue that constitutes by ferrite and pearlite, given during oxygen-free boron as the good machinability of the powder of pearlitic structrure.
It is machine-processed as follows that this ferritic structure generates.That is, the fusing point of boron compound (boron oxide) is about 500 ℃, reaches the boron compound that said temperature then liquefied during sintering and forms tunicle at carbon surrounding, and blocking-up carbon is to the diffusion of matrix.As a result, compare, formed pearlitic structrure morely with ferritic structure.
Therefore, when generating the raising machinability effect that is caused for the ferrite that keeps this boron oxide to cause, only improve the method for the intensity of necessary position, the inventor inquires into.Be the method for the intensity of sintered component generally as improving iron, known to sintered body enforcement copper infiltration.The copper infiltration is to utilize capillary force copper to be filled in the pore of sintered body and improve the density of sintered body and improve quenching degree by copper to the diffusion of matrix, improves the method for the intensity of the sintered body behind the infiltration thus.The inventor has been actually in the formed body that is made of the mixed-powder that contains iron, carbon and boron oxide and its sintered body infiltration copper or copper alloy.As a result, find that not only above-mentioned sintered density improves and the quenching degree raising causes intensity to improve, and because the intensity raising of following phenomenon sintered body behind infiltration.
That is, place the infiltration material that copper powders may or copper alloy powder are shaped and obtain on the formed body of the mixed-powder that contains iron, carbon and boron oxide, when carrying out sintering (infiltration), sintering temperature will form aqueous boron oxide tunicle at carbon surrounding if reach about 500 ℃.But sintering temperature further rises, and the fusing point that reaches copper or copper alloy is when (for example, when using copper with simple substance powder (flavor powder), being about 1083 ℃), and the copper of fusion or copper alloy immerse in the pore, and attack packets is round the tunicle of the boron compound of carbon, with its destruction.In addition, even the diffusion of carbon to the iron-based body also takes place near the fusing point of copper or copper alloy,, can freely in matrix, spread in case therefore carbon is released from the tunicle of boron compound.For this reason, at infiltration on the position of copper, carbon is fully to matrix diffusion, matrix is based on pearlitic structrure as a result, intensity improves.Relative therewith, at infiltration beyond the position of copper, formed the matrix that constitutes by ferrite and pearlitic structrure, kept good machinability.
The manufacture method that the 1st iron of the present invention is sintered component is based on above-mentioned opinion and finishes, it is characterized in that, on at least a portion that iron is sintered component with the surface of the sintered body of the powder compact of powder or this powder compact, the infiltration material that placement obtains shaping of metal powders, sintering temperature more than the fusing point of temperature more than the diffusion temperature of carbon and infiltration material is placed with the above-mentioned powder compact or the sintered body of above-mentioned infiltration material, above-mentioned iron is the sintered component powder, be to be that the iron of having removed powdered graphite the mixture of powders used of agglomerated material is mixture of powders with respect to the iron that behind sintering, presents pearlitic structrure, in match ratio, add the boron oxide of 0.01～1.0 quality %, with the powder of the powdered graphite of 0.1～2.0 quality %, above-mentioned metal dust is copper powders may or copper alloy powder.
In addition, the same opinion of manufacture method that it is sintered component that the inventor utilizes with above-mentioned the 1st iron is for being that the additive method of infiltration copper or copper alloy is inquired in the agglomerated material at iron.As a result, draw following opinion: by making iron is the phosphorus that contains ormal weight in the mixed-powder, can realize ferritic reinforcement efficiently, can further improve machinability.That is,, can't fully obtain the hardness of matrix if the phosphorus content deficiency then lacks ferritic invigoration effect.Relative therewith, its content is too much, and then the generation of Fe-P liquid phase increases in the sintering, the sand mold that formed body easily takes place in the sintering collapse (type く ず れ).
The manufacture method that the 2nd iron of the present invention is sintered component is based on above-mentioned opinion and finishes, it is characterized in that, be sintered component with the powder compact of powder or heat this powder compact and at least a portion on the surface of the sintered body that obtains at iron, the infiltration material that placement obtains shaping of metal powders, sintering temperature more than the fusing point of temperature more than the diffusion temperature of carbon and infiltration material is placed with the above-mentioned powder compact or the sintered body of above-mentioned infiltration material, above-mentioned iron is the sintered component powder, be by quality ratio by P:0.1～1.0%, B:0.003～0.31%, O:0.007～0.69%, C:0.1～2.0%, surplus is the powder that Fe and unavoidable impurities constitute, and above-mentioned metal dust is copper powders may or copper alloy powder.
The 3rd iron is that the manufacture method of sintered component is characterised in that, in above-mentioned the 2nd manufacture method, further contains the Cu of 1.0～5.0 quality %.By so containing Cu, improve intensity when can realize keeping machinability.Though Cu also spreads in matrix and strengthens, Cu contains quantity not sufficient 1.0 quality %, then lacks its effect.On the other hand, Cu content surpasses 5 quality %, then generating soft Cu phase intensity reduces, simultaneously the Cu liquid phase that produces during sintering causes dimensional contraction, occur being easy to causing that to the Cu swelling that the Cu of Fe matrix diffusion causes small pucker ﹠ bloat takes place the each several part at goods, the deviation of the change in size of goods integral body increase as a result, dimensional accuracy variation with shrinking owing to liquid phase.
Being the manufacture method of sintered component for iron of the present invention above, is sintered component but the invention still further relates to the iron that utilizes these manufacture methods to obtain.In addition, above-mentioned manufacture method of the present invention can be applicable to the manufacturing of sintered mechanical part especially, for example, possessing the sintered mechanical part that is used for by the bolt hole of bolted banding, by to implementing above-mentioned infiltration with the contact portion of bolt, can make its hardness is 200～600HV, can fully guarantee intensity, part is not in addition implemented infiltration, can make its hardness is 100～190HV, can fully guarantee machinability.
Utilizing iron of the present invention is the manufacturing technology of sintered component, when manufacturing iron is sintered component, at optimization iron is that sintered component is with in the composition of powder, only will be applied to necessary position, and can obtain not only realizing with high standards intensity and machinability thus, also only on each necessary position, give the sintered component of these characteristics by the infiltration material that copper or copper alloy constitute.
Description of drawings
Fig. 1 is the front view of expression as the bearing cap of automobile component.
Fig. 2 is the front view of the use form of expression bearing cap shown in Figure 1.
Fig. 3 is the process chart of the manufacture method of expression bearing cap shown in Figure 2.
Fig. 4 is the photo of organizing of the bearing cap behind the sintering, (a) expression infiltration part among the figure, (b) the non-infiltration part of expression.
Symbol description
10 bearing caps
The 10a recess
The part that 10b contacts with the bolt supporting surface
11 cylinder block
The 11a recess
12 bearings
The last side bearing of 12a
Side bearing under the 12b
13 bent axles
14a, 14b bolt
The specific embodiment
Fig. 1 is the front view of the middle bearing caps 10 that use such as expression automobile component.This bearing cap 10 in use, as shown in Figure 2, use in order on the sidewall of the cylinder block 11 of car engine, bent axles to be installed by bearing 12, after contact-making surface position with the last side bearing 12a and the bearing 12b that gets off is coincide, install from the top of last side bearing 12a, be fixed on the cylinder block 11 by bolt 14a, 14b banding.In addition, the common recess 11a with the cylinder block 11 that is made of aluminium alloy of the recess 10a of bearing cap 10 is as shown in Figure 1 processed by incrustation integratedly.
Consider the processing form (incrustation processing) of this bearing cap 10 and use form (bolted), when requiring to give the good machinability of above-mentioned recess 10a, also require the part 10b that contacts with the bolt supporting surface to have good intensity.Considering that these require characteristic, is that example illustrates that iron of the present invention is the preferred implementation that the manufacturing technology of sintered component relates to below with the bearing cap.
Fig. 3 is the process chart of the manufacture method of expression bearing cap shown in Figure 2.In the figure, at first utilizing iron is sintered component powder preparation powder compact, simultaneously with copper powders may or copper alloy powder shaping infiltration material.As mentioned above, the objective of the invention is to final necessary position intensity and machinability of giving sintered body respectively.Intensity can by in aftermentioned sintering (infiltration) operation in powder compact infiltration copper or copper alloy give.For this reason, as the prerequisite of giving intensity, it is crucial selecting to give in advance the sintered body part machinability of not carrying out infiltration according to its material.
For this viewpoint, when manufacturing iron was sintered component, above-mentioned iron was that the sintered component powder is:
(1) be that the iron of having removed powdered graphite the powdered graphite used of agglomerated material is mixture of powders with respect to the iron that behind sintering, presents pearlitic structrure, in mixing ratio, the powder (following abbreviate as sometimes " mixed-powder 1 ") of the boron oxide of interpolation 0.01～1.0 quality % and the powdered graphite of 0.1～2.0 quality %; Or
(2) by quality ratio, by P:0.1～1.0%, B:0.003～0.31%, O:0.007～0.69%, C:0.1～2.0%, surplus is the powder (following abbreviate as sometimes " mixed-powder 2 ") that Fe and unavoidable impurities constitute.
Narrate the qualification reason of each composition of mixed-powder 1,2 below.
(the qualification reason of each composition of mixed-powder 1)
In order to give sintered body good machinability, make matrix behind the sintering for by ferrite and pearlite but not the tissue that pearlite constitutes, as kollag free graphite to be disperseed be important.For this reason, must limit iron is the carbon amount of agglomerated material with powder.In sintered body, obtain free graphite when making matrix be the tissue of ferrite main body, adopted in the past and under the diffusion temperature of not enough carbon, carry out sintering, do not make carbon be diffused in method in the matrix, but because sintering temperature is low, the growth of the neck that forms between the matrix iron powder (ネ ッ Network) is insufficient, sintered body intensity significantly reduces, and this is a problem.
For this reason, the inventor inquires into for the method for the dispersion of low-intensityization that prevents sintered body and realization free graphite.The result, confirmed by the boron oxide that contains 0.01～1.0 quality %, the powdered graphite of 0.1～2.0 quality %, even sintering temperature is the above following time of temperature of diffusion temperature of carbon, can make tissue, the acquisition good machinability of matrix for constituting of sintered body by utilizing boron oxide to suppress carbon to the diffusion of matrix, and can make the neck that forms between the iron powder fully grow up, obtain the intensity of regulation by ferrite and pearlite.
At this, narrate for the qualification reason of boron oxide content.As mentioned above, boron oxide content lacks and suppresses the diffusion effect of graphite to matrix if less than 0.01 quality % even then boron oxide liquefies near 500 ℃, but because its amount is not enough, can't thoroughly surround around the graphite, and matrix is called the tissue of pearlite main body.Even and content surpasses 1.0 quality %, then not only can't obtain better carbon diffusion and suppress effect, and because boron oxide residues in the matrix in a large number, sintered body intensity reduces.Therefore, the content with boron oxide is made as 0.01～1.0 quality %.
In addition, narrate for the qualification reason of powdered graphite content.As mentioned above, the content corresponding to boron oxide contains powdered graphite.Its content is as if less than 0.1 quality %, and the carbon amount that then spreads in matrix is very few, not only can't obtain desired intensity, and the amount of the free graphite that does not spread is few, can't obtain machinability and improve effect.On the other hand, if the addition of powdered graphite surpasses 2.0 quality %, then can't fully suppress the diffusion of carbon to matrix, matrix is a pearlite.Therefore, the content with graphite is made as 0.1～2.0 quality %.
(the qualification reason of each composition of mixed-powder 2)
If P:P contains quantity not sufficient 0.1 quality %, then lack ferritic invigoration effect, the result can't significantly improve the hardness of matrix.On the other hand, if P content surpasses 1.0 quality %, then the generation of Fe-P liquid phase increases in the sintering, and the sand mold that the press-powder body in the sintering easily takes place collapses.Therefore, the content with P is made as 0.1～1.0 quality %.Though can add P in the mode of simple substance powder, because strong toxicity preferably adds in the mode of Fe-P alloyed powder.
B, O: contain o and O by adding in the mode of boron oxide.B:0.003～0.31 quality %, O:0.007～0.69 quality % is as B
2O
3Be 0.01～1.0 quality %,, then can't suppress the diffusion of carbon during sintering to matrix if be lower than lower limit separately.On the other hand,, can't expect that not only better carbon diffusion suppresses effect, and boron oxide remains in a large number in the matrix, the intensity of sintered body is reduced if surpass separately the upper limit.Therefore, the addition that the addition of B is made as 0.003～0.31 quality %, O is made as 0.007～0.69 quality %.
Mode with powdered graphite is added C:C, if but its content less than 0.1 quality %, the carbon amount that then spreads in matrix is very few, not only can't obtain desired intensity, and the free graphite amount that does not spread is few, can't obtain the effect of improving of machinability.On the other hand, if the addition of powdered graphite surpasses 2.0 quality %, then can't fully suppress the diffusion of C to matrix, matrix is a pearlite.Therefore, the content with C is made as 0.1～2.0 quality %.
Using above-mentioned iron is sintered component with powder (mixed-powder 1 or mixed-powder 2), as shown in the drawing when prepare the powder compact of bearing cap shape shown in Figure 3, prepares the infiltration material that copper powders may or copper alloy powder shaping are obtained.At this, for example can use the alloy that constitutes by copper and cobalt as copper alloy.
Then, the part that contacts with the bolt supporting surface when making infiltration material be immersed in the bolt banding is placed infiltration material as shown in Figure 3 on powder compact, carry out sintering (infiltration) under this state.The laying state that it should be noted that infiltration material is not limited to form shown in Figure 3, by the attitude of appropriate change powder compact in stove, also can place infiltration material near any surface the position that needs the infiltration powder compact.
And then, at carbon to carrying out sintering more than the temperature more than the diffusion temperature of matrix (about 850～900 ℃) and under the temperature more than the fusing point of infiltration material (when using copper with simple substance, being more than 1083 ℃ for example) as infiltration material.It should be noted that for realize copper to the intensity that the diffusion of iron-based body causes improve and iron powder between the intensity that causes of the abundant growth of the neck that forms improve, and prevent the volatilization of boron oxide, sintering temperature is located in 1050～1150 ℃ the scope.In addition, the sintering environment is made as the reducibility gas environment.
In this sintering circuit, if at first sintering temperature reaches about 500 ℃, then iron is that sintered component liquefies with boron oxide contained in the powder, and boron oxide surrounds carbon surrounding, forms tunicle, and blocking-up carbon is to the diffusion of matrix.Then, if sintering temperature reaches the fusing point of infiltration material, then the copper of fusion etc. immerses in the pore, and attack packets is destroyed this tunicle round the tunicle of the boron oxide of carbon.Thus,, then can freely in matrix, spread if carbon is released from the tunicle of boron oxide, at infiltration on the position of copper etc., fully to the matrix diffusion, matrix becomes pearlitic structrure to carbon as a result, the intensity of sintered body partly improves.
In addition, at infiltration on the position of copper or copper alloy because capillary force, copper etc. are invaded to pore, the filling of pore has caused the raising of sintered density, also will improve intensity thus.And, be immersed into copper in the pore etc. and further in matrix, spread, improve quenching degree, also will improve intensity thus.
Thus, the result can obtain a kind of bearing cap, its cylinder block and possess good machinability through the recess of Surface Machining, and the part that contacts with the bolt supporting surface that has applied equivalent stress when using simultaneously possesses good intensity.It should be noted that before infiltration, to be provided with bolt hole in the example shown in Figure 3, but the present invention is not limited to this form, also can after being machined in infiltration, bolt hole be set.
Above for the present invention can be preferred embodiment an example.In above-mentioned example, be to place infiltration material on the powder compact that constitutes with powder of sintered component and carried out sintering by iron, but preferably before this is placed prior under 400～950 ℃ temperature the presintering powder formed body.Utilizing this vacation sintering to remove de-iron in advance is the shaping lubricant of sintered component in the powder, can improve infiltration thus.
In addition, be that sintered component is used in the powder (mixed-powder 1 or mixed-powder 2) at iron, also can further contain boron nitride.At this moment, be defined in 0.06～2.25 quality % with the content of the boron nitride in the powder, do not reduce the intensity of matrix and just can bring into play chip breaking (チ ッ プ Block レ one キ Application グ) effect and solid lubricant effect, can further improve machinability by being sintered component with iron.That is, boron nitride contain quantity not sufficient 0.06 quality % the time, lack above-mentioned effect, when surpassing 2.25 quality %, the intensity of matrix descends.It should be noted that, interpolation form as boron nitride, specially permit No. 3413628 communique and the record of TOHKEMY 2000-144350 communique as Japan, preferred less expensive powder (mixed-powder of boron oxide and boron nitride) 0.1～2.5 quality % that adds the boron oxide that contains 10～40 quality % adds with boron oxide.
Embodiment
(the copper infiltration is to the influence of machinability and intensity)
As material powder, prepare to contain Cu:3.0 quality %, C:1.0 quality %, B with mass ratio
2O
3: 0.7 quality %, surplus is that the iron of Fe and unavoidable impurities is the sintered component powder, mix 30 minutes with V-Mixer after, the mixed-powder press-powder is configured as density 6.7g/cm
3, obtain the powder compact of bearing cap shape as shown in Figure 3.In addition, press-powder shaping fine copper powder obtains 2 infiltration materials as shown in Figure 3.
Then, in the reproducibility environment, behind 690 ℃ of above-mentioned powder compacts of following presintering, in order on the presintering body and part that the bolt supporting surface contacts, to immerse infiltration material, on the presintering body, place infiltration material with form shown in Figure 3, carrying out sintering (infiltration) under this state, in the reproducibility environment, under 1130 ℃.
Fig. 4 is the photo of organizing of the bearing cap behind the sintering, (a) expression infiltration part among the figure, (b) the non-infiltration part of expression.Shown in Fig. 4 (a), for the infiltration part, matrix is pearlite, because copper infiltration pore disappears.For this reason, be speculated as the material that has obtained good strength.As the result of hardness test, matrix hardness is 250HV, and this conforms to the application's claim 4, has obtained good hardness.Therefore, in the infiltration part,, also obtained the intensity that can fully tolerate even can confirm to contact the time with the bolt seating surface.
Relative therewith, shown in Fig. 4 (b), for non-infiltration part, matrix is ferrite and pearlite.For this reason, obtained good machinability.It should be noted that for non-infiltration part and also carried out hardness test, but matrix hardness is 140HV, conforms to the application's claim 4.Therefore, in non-infiltration part (recess that contains bearing cap), fail to obtain the such hardness of infiltration part, but can confirm to obtain usually and the recess of the cylinder block that constitutes by the aluminium alloy required sufficient machinability of Surface Machining integratedly.
As mentioned above, can provide according to the present invention not only with high standard realize intensity and machinability, And the iron of only giving these characteristics to each needed position is sintered component. Therefore, consider To being sintered component applicable to the various iron that use in automobile and the automotive bicycle, the present invention Promising.
Claims (5)
1. manufacture method that iron is sintered component, it is sintered component with the powder compact of powder or heats this powder compact and at least a portion on the surface of the sintered body that obtains at iron, the infiltration material that placement obtains shaping of metal powders, sintering temperature more than the fusing point of temperature more than the diffusion temperature of carbon and infiltration material is placed with the above-mentioned powder compact or the sintered body of above-mentioned infiltration material, it is characterized in that, above-mentioned iron is the sintered component powder, be to be that the iron of having removed powdered graphite the mixture of powders used of agglomerated material is mixture of powders with respect to the iron that behind sintering, presents pearlitic structrure, in mixing ratio, add the boron oxide of 0.01～1.0 quality %, with the powder of the powdered graphite of 0.1～2.0 quality %, above-mentioned metal dust is copper powders may or copper alloy powder.
2. manufacture method that iron is sintered component, it is sintered component with the powder compact of powder or heats this powder compact and at least a portion on the surface of the sintered body that forms at iron, the infiltration material that placement obtains shaping of metal powders, sintering temperature more than the fusing point of temperature more than the diffusion temperature of carbon and infiltration material is placed with the above-mentioned powder compact or the sintered body of above-mentioned infiltration material, it is characterized in that, above-mentioned iron is the sintered component powder, be by quality ratio by P:0.1～1.0%, B:0.003～0.31%, O:0.007～0.69%, C:0.1～2.0%, surplus is the powder that Fe and unavoidable impurities constitute, and above-mentioned metal dust is copper powders may or copper alloy powder.
3. iron as claimed in claim 2 is the manufacture method of sintered component, it is characterized in that, further contains the Cu of 1.0～5.0 quality %.
4. utilizing the iron that each described manufacture method obtains in the claim 1～3 is sintered component.
5. sintered mechanical part, it is to possess the sintered mechanical part that is used for by the bolt hole of bolted banding, it is characterized in that, and the hardness of the part that contacts with above-mentioned bolt supporting surface is 200～600HV, and the hardness of part in addition is 100～190HV.
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| JP2005074553A JP4497368B2 (en) | 2005-03-16 | 2005-03-16 | Manufacturing method of iron-based sintered member and iron-based sintered member obtained thereby |
| JP2005074553 | 2005-03-16 |
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| CN1833799A true CN1833799A (en) | 2006-09-20 |
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| CN112444151A (en) * | 2019-09-03 | 2021-03-05 | 广州力及热管理科技有限公司 | Metal oxide slurry for manufacturing capillary structure of uniform temperature plate element |
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| JP5260913B2 (en) * | 2007-08-03 | 2013-08-14 | 株式会社神戸製鋼所 | Iron-based mixed powder for powder metallurgy and sintered iron powder |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPH06145720A (en) * | 1992-11-12 | 1994-05-27 | Mitsubishi Materials Corp | Double layer valve seat made of copper-infiltrated iron series sintered alloy for internal combustion engine |
| JP3413628B2 (en) * | 1996-03-05 | 2003-06-03 | 日立粉末冶金株式会社 | Iron-based powder mixture for obtaining graphite-dispersed iron-based sintered material |
| JP3325173B2 (en) * | 1995-12-08 | 2002-09-17 | 日立粉末冶金株式会社 | Modification method of iron-based sintered material |
| JP3410326B2 (en) * | 1997-04-25 | 2003-05-26 | 日立粉末冶金株式会社 | Method for producing iron-based sintered alloy, iron-based sintered alloy produced by this method, and bearing cap |
| JP3537126B2 (en) * | 1998-11-17 | 2004-06-14 | 日立粉末冶金株式会社 | Free-cutting iron-based sintered alloy and method for producing the same |
| US6514307B2 (en) * | 2000-08-31 | 2003-02-04 | Kawasaki Steel Corporation | Iron-based sintered powder metal body, manufacturing method thereof and manufacturing method of iron-based sintered component with high strength and high density |
| JP2002363610A (en) * | 2001-04-26 | 2002-12-18 | Ntn Corp | Copper infiltrated ferro-phosphorus powder metal |
| US6676894B2 (en) * | 2002-05-29 | 2004-01-13 | Ntn Corporation | Copper-infiltrated iron powder article and method of forming same |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN112444151A (en) * | 2019-09-03 | 2021-03-05 | 广州力及热管理科技有限公司 | Metal oxide slurry for manufacturing capillary structure of uniform temperature plate element |
| CN112444151B (en) * | 2019-09-03 | 2022-01-11 | 广州力及热管理科技有限公司 | Metal oxide slurry for manufacturing capillary structure of uniform temperature plate element |
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| JP2006257471A (en) | 2006-09-28 |
| CN100463746C (en) | 2009-02-25 |
| JP4497368B2 (en) | 2010-07-07 |
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