JP2013253302A - Method for manufacturing sintering-diffusion-bonded component - Google Patents
Method for manufacturing sintering-diffusion-bonded component Download PDFInfo
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- JP2013253302A JP2013253302A JP2012130744A JP2012130744A JP2013253302A JP 2013253302 A JP2013253302 A JP 2013253302A JP 2012130744 A JP2012130744 A JP 2012130744A JP 2012130744 A JP2012130744 A JP 2012130744A JP 2013253302 A JP2013253302 A JP 2013253302A
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本発明は、異なる材料を焼結拡散接合により接合した焼結拡散接合部品の製造方法に関するものである。 The present invention relates to a method for manufacturing a sintered diffusion bonded component in which different materials are bonded by sintered diffusion bonding.
このような焼結拡散接合部品である可動鉄心が特許文献１〜３等に開示されている。この可動鉄心は、炭素鋼からなる耐摩耗性材料で構成された軸部材と、この軸部材の一端側に設けられ、内孔を有する形状であって、Ｆｅ系金属からなる外周部材とを備えるものである。この可動鉄心は、外周部材の形状とされた圧粉体と軸部材とを一体化させる一体化工程を行った後、圧粉体と軸部材とを加熱する焼結工程を行うことにより、圧粉体を焼結させて外周部材を形成するとともに、圧粉体と軸部材とを焼結拡散接合により接合することで製造される。 A movable iron core which is such a sintered diffusion bonding component is disclosed in Patent Documents 1 to 3 and the like. The movable iron core includes a shaft member made of a wear-resistant material made of carbon steel, and an outer peripheral member made of an Fe-based metal that is provided on one end side of the shaft member and has an inner hole. Is. This movable iron core is subjected to a sintering process in which the green compact and the shaft member are heated after performing an integration process in which the green compact having the shape of the outer peripheral member and the shaft member are integrated. The outer peripheral member is formed by sintering the powder, and the green compact and the shaft member are joined by sintered diffusion bonding.
ところで、上述のように、炭素鋼からなる耐摩耗性材料とＦｅ系金属からなる圧粉体を焼結拡散接合により接合した焼結拡散接合部品を製造する際では、焼結工程後に除冷を実施したとしても、耐摩耗性材料には焼きが入り、硬化してしまう。 By the way, as described above, when manufacturing a sintered diffusion bonding part in which a wear-resistant material made of carbon steel and a green compact made of Fe-based metal are bonded by sintering diffusion bonding, cooling is performed after the sintering process. Even if implemented, the wear resistant material will burn and harden.
このため、後工程で耐摩耗性材料の表層を切削加工する必要がある場合、切削加工前に焼鈍工程を実施することにより、耐摩耗性材料の硬度を落とさなければならず、焼鈍工程を実施しなくても切削加工ができることが望まれていた。 For this reason, when it is necessary to cut the surface layer of the wear-resistant material in the subsequent process, the hardness of the wear-resistant material must be reduced by carrying out the annealing process before cutting, and the annealing process is carried out. It has been desired that cutting can be performed without the need.
本発明は上記点に鑑みて、焼鈍工程を実施しなくても、耐摩耗性材料の表層を切削加工できるようにすることを目的とする。 In view of the above points, an object of the present invention is to enable cutting of a surface layer of an abrasion-resistant material without performing an annealing step.
上記目的を達成するため、請求項１に記載の発明では、
耐摩耗性材料と、フェライト化元素を含有する圧粉体とを一体化させる一体化工程（１０１）と、
一体化工程後に、耐摩耗性材料と圧粉体とを脱炭性雰囲気下で加熱することにより、耐摩耗性材料の表層に脱炭を生じさせてフェライト相を形成する脱炭工程（１０２）と、
脱炭工程後に、耐摩耗性材料と圧粉体とを加熱することにより、圧粉体を焼結させるとともに耐摩耗性材料と圧粉体とを焼結拡散接合し、さらに、耐摩耗性材料の表層にフェライト化元素が拡散することによってフェライト相の形成範囲を拡張させて耐摩耗性材料の表面に軟化層（３３）を形成する焼結工程（１０３）と、
焼結工程後に、耐摩耗性材料の表層を切削加工する切削工程（１０４）とを有することを特徴としている。
In order to achieve the above object, in the invention described in claim 1,
An integration step (101) for integrating the wear-resistant material and the green compact containing the ferritic element;
After the integration step, the decarburization step (102) in which the wear resistant material and the green compact are heated in a decarburizing atmosphere to cause decarburization in the surface layer of the wear resistant material to form a ferrite phase. When,
After the decarburization process, the wear-resistant material and the green compact are heated to sinter the green compact and to sinter diffusion-bond the wear-resistant material and the green compact. A sintering step (103) for extending the formation range of the ferrite phase by diffusing the ferritic element into the surface layer, and forming a softening layer (33) on the surface of the wear-resistant material;
And a cutting step (104) for cutting the surface layer of the wear-resistant material after the sintering step.
これによれば、焼結工程で、耐摩耗性材料の表面に軟化層が形成されるので、焼結工程後に焼鈍工程を実施しなくても、耐摩耗性材料の表層を切削加工することができる。 According to this, since the softening layer is formed on the surface of the wear resistant material in the sintering process, the surface layer of the wear resistant material can be cut without performing the annealing process after the sintering process. it can.
なお、この欄および特許請求の範囲で記載した各手段の括弧内の符号は、後述する実施形態に記載の具体的手段との対応関係を示す一例である。 In addition, the code | symbol in the bracket | parenthesis of each means described in this column and the claim is an example which shows a corresponding relationship with the specific means as described in embodiment mentioned later.
以下、本発明の実施形態について説明する。
（第１実施形態）
第１実施形態では、車両用燃料噴射装置のソレノイド式インジェクタのアーマチャ（可動鉄心）の製造方法について説明する。
Hereinafter, embodiments of the present invention will be described.
(First embodiment)
1st Embodiment demonstrates the manufacturing method of the armature (movable iron core) of the solenoid type injector of the fuel injection device for vehicles.
まず、アーマチャを備える電磁弁の構造について説明する。図１、２に示すように、アーマチャ３は、軸部材１とこの軸部材１の一端側に設けられた外周部材２とを有している。この軸部材１の他端側には図示しない弁座と離接する図示しない弁体が設けられている。外周部材２は軸部材１の長手方向に対して垂直な方向に延びた扁平形状である。 First, the structure of a solenoid valve provided with an armature will be described. As shown in FIGS. 1 and 2, the armature 3 includes a shaft member 1 and an outer peripheral member 2 provided on one end side of the shaft member 1. On the other end side of the shaft member 1 is provided a valve body (not shown) that is in contact with a valve seat (not shown). The outer peripheral member 2 has a flat shape extending in a direction perpendicular to the longitudinal direction of the shaft member 1.
そして、図１に示す電磁弁１０は、軸部材１の長手方向においてアーマチャ３と対向する位置に固定鉄心４が配置されており、この固定鉄心４にはソレノイドコイル５が巻回されている。この電磁弁１０においては、固定鉄心４に巻回されたソレノイドコイル５に電流を供給することによって、アーマチャ３が固定鉄心４側に磁力吸引されて弁が開くとともに、固定鉄心４に巻回されたソレノイドコイル５に流れる電流を遮断することによって、図示しないばねの復帰力によりアーマチャ３が元の位置に復帰し、弁が閉じられる。 In the electromagnetic valve 10 shown in FIG. 1, a fixed iron core 4 is disposed at a position facing the armature 3 in the longitudinal direction of the shaft member 1, and a solenoid coil 5 is wound around the fixed iron core 4. In this electromagnetic valve 10, by supplying current to the solenoid coil 5 wound around the fixed iron core 4, the armature 3 is attracted to the fixed iron core 4, and the valve is opened, and the armature 3 is wound around the fixed iron core 4. By shutting off the current flowing through the solenoid coil 5, the armature 3 returns to the original position by the return force of a spring (not shown), and the valve is closed.
ここで、アーマチャ３は、異なる材料からなる軸部材１と外周部材２とが焼結拡散接合してなる拡散接合部品である。 Here, the armature 3 is a diffusion bonded component formed by sintering diffusion bonding the shaft member 1 and the outer peripheral member 2 made of different materials.
軸部材１は、硬度がＨｖ６００以上の炭素鋼からなる耐摩耗性材料で構成されている。この耐摩耗性材料としては、例えばＪＩＳ規格のＳＫＨ５１材、ＳＫＨ２材等の高速度工具鋼や、例えばＪＩＳ規格のＳＵＪ２材等の軸受鋼や、例えばＪＩＳ規格のＳＫＤ１１材等の合金工具鋼が挙げられる。 The shaft member 1 is made of an abrasion-resistant material made of carbon steel having a hardness of Hv600 or higher. Examples of the wear-resistant material include high speed tool steel such as JIS standard SKH51 material and SKH2 material, bearing steel such as JIS standard SUJ2 material, and alloy tool steel such as JIS standard SKD11 material. It is done.
外周部材２は、Ｆｅを主成分とするＦｅ系金属からなる圧粉体を焼結させたものである。圧粉体は、原料粉末を圧粉成形したものである。この原料粉末としては、例えば、Ｆｅ−Ｓｉ−Ｐ系や、Ｆｅ−Ｓｉ系の組成を有する軟磁性粉末が挙げられる。ＳｉおよびＰは焼結拡散接合を形成するための元素であるが、これらの元素のうちＳｉは、耐摩耗性材料に拡散した場合に拡散した領域の組織をフェライト相化するフェライト化元素でもある。 The outer peripheral member 2 is obtained by sintering a green compact made of Fe-based metal whose main component is Fe. The green compact is obtained by compacting a raw material powder. Examples of the raw material powder include Fe-Si-P-based and soft magnetic powder having an Fe-Si-based composition. Si and P are elements for forming sintered diffusion bonding, and among these elements, Si is also a ferritizing element that causes the structure of the diffused region to become a ferrite phase when diffused into the wear-resistant material. .
次に、アーマチャ３の製造方法について説明する。 Next, a method for manufacturing the armature 3 will be described.
図３に示すように、軸部材１と外周部材２の形状とされた圧粉体とを組み付ける組み付け工程１０１を行う。この組み付け工程１０１が特許請求の範囲に記載の一体化工程に相当する。 As shown in FIG. 3, the assembly | attachment process 101 which assembles the green compact made into the shape of the shaft member 1 and the outer peripheral member 2 is performed. This assembly process 101 corresponds to the integration process described in the claims.
具体的には、耐摩耗性材料からなる軸部材１を用意する。また、内孔を有する外側部材２の形状となるように、原料粉末を圧粉成形して得られた圧粉体を用意する。このとき、圧粉体には成形潤滑剤が含まれている。この成形潤滑剤は、熱処理によってＣＯ２とＨ２Ｏに分解される有機化合物からなるものである。この成形潤滑剤としては、ワックス系、ステアリン酸系等の一般的な金属粉末の圧粉成形用の潤滑剤を用いることができる。そして、得られた圧粉体の内孔に軸部材１を嵌合して一体化する。 Specifically, a shaft member 1 made of an abrasion resistant material is prepared. Moreover, the green compact obtained by compacting raw material powder so that it may become the shape of the outer member 2 which has an inner hole is prepared. At this time, the green compact contains a molding lubricant. This molding lubricant is made of an organic compound that is decomposed into CO 2 and H 2 O by heat treatment. As this molding lubricant, a lubricant for compacting metal powder such as wax and stearic acid can be used. And the shaft member 1 is fitted and integrated in the inner hole of the obtained green compact.
その後、組み付け後の軸部材１と圧粉体とを加熱することにより、圧粉体中の成形潤滑剤を分解させる脱脂工程１０２を行う。加熱温度は、成形潤滑剤の分解温度、例えば、６００℃である。このとき、一般的な脱脂工程では、成形潤滑剤の分解によって生成するガスを加熱雰囲気から排除するが、本実施形態では、成形潤滑剤の分解によって生成するＣＯ２とＨ２Ｏとを加熱雰囲気中に残した状態とすることで、ＣＯ２とＨ２Ｏとが存在する加熱雰囲気下で軸部材１と圧粉体とを加熱する。例えば、圧粉体中の成形潤滑剤の添加量を、圧粉体の成形に必要な添加量よりも増大させることで、ＣＯ２とＨ２Ｏとを加熱雰囲気中に残した状態とすることが可能となる。これは、成形潤滑剤の分解によって加熱雰囲気中に放出されるＣＯ２とＨ２Ｏとが増大すると、加熱雰囲気中のＣＯ２とＨ２Ｏとが全て排除されずに残された状態になりやすいからである。 Then, the degreasing process 102 which decomposes | disassembles the shaping | molding lubricant in a green compact is performed by heating the shaft member 1 and green compact after an assembly | attachment. The heating temperature is a decomposition temperature of the molded lubricant, for example, 600 ° C. At this time, in a general degreasing process, gas generated by decomposition of the molding lubricant is excluded from the heating atmosphere. In this embodiment, CO 2 and H 2 O generated by decomposition of the molding lubricant are heated in the heating atmosphere. The shaft member 1 and the green compact are heated in a heating atmosphere in which CO 2 and H 2 O exist by being left in the inside. For example, the amount of molding lubricant added in the green compact is increased beyond that required for compacting the green compact, leaving CO 2 and H 2 O in the heated atmosphere. Is possible. This is because, if the CO 2 released into the heating atmosphere by decomposition of the molded lubricant and H 2 O is increased, ready to CO 2 and of H 2 O in a heated atmosphere is left without being eliminated all It is easy.
その後、組み付け後の軸部材１と圧粉体とを加熱することにより、圧粉体を焼結させて外周部材２とするとともに軸部材１と外周部材２とを拡散接合する焼結工程１０３を行う。このときの加熱温度は、例えば、１１００℃〜１３００℃である。 Thereafter, the assembled shaft member 1 and the green compact are heated to sinter the green compact to form the outer peripheral member 2, and at the same time, a sintering step 103 for diffusion bonding the shaft member 1 and the outer peripheral member 2. Do. The heating temperature at this time is 1100 degreeC-1300 degreeC, for example.
その後、軸部材１の表層を切削加工する切削工程１０４を行う。このとき、焼結工程後の軸部材１の表層は、切削加工ができるほど硬度が低下しているので、焼鈍工程を実施しなくても、軸部材１の表層を切削加工することができる。このようにしてアーマチャ３が製造される。 Then, the cutting process 104 which cuts the surface layer of the shaft member 1 is performed. At this time, since the hardness of the surface layer of the shaft member 1 after the sintering step is reduced to the extent that cutting can be performed, the surface layer of the shaft member 1 can be cut without performing the annealing step. In this way, the armature 3 is manufactured.
次に、軸部材１の表層の硬度が低下するメカニズムについて、図４〜７を用いて説明する。図４〜７は図１中の破線で囲まれた領域Ａ１に相当する。 Next, the mechanism by which the hardness of the surface layer of the shaft member 1 is lowered will be described with reference to FIGS. 4 to 7 correspond to a region A1 surrounded by a broken line in FIG.
組み付け工程後であって、脱脂工程１０２の前の段階では、図４に示すように、軸部材１は、全領域の組織がγ相となっている。また、外周部材２を形成するための圧粉体２０には、Ｓｉ、Ｐ元素や、成形潤滑剤２１が含まれている。 After the assembly process and before the degreasing process 102, as shown in FIG. 4, the shaft member 1 has a γ phase in the entire region. The green compact 20 for forming the outer peripheral member 2 contains Si and P elements and a molding lubricant 21.
そして、脱脂工程１０２では、図５に示すように、成形潤滑剤２１から生成した脱炭性ガスであるＣＯ２とＨ２Ｏとを加熱雰囲気中に残した状態で、軸部材１と圧粉体２０とを加熱するので、軸部材１の表面でＣ元素の抜け（脱炭）が生じる。これにより、軸部材１の表層の組織がγ相からα相（フェライト相）に変化する。このフェライト相の軸部材１の表面からの厚さは、例えば、５０μｍである。 Then, in the degreasing step 102, as shown in FIG. 5, while leaving the CO 2 and H 2 O is a decarburizing gas generated from the molded lubricant 21 in the heating atmosphere, the shaft member 1 and the dust Since the body 20 is heated, C element escape (decarburization) occurs on the surface of the shaft member 1. Thereby, the structure of the surface layer of the shaft member 1 changes from the γ phase to the α phase (ferrite phase). The thickness of the ferrite phase shaft member 1 from the surface is, for example, 50 μm.
その後、焼結工程１０３では、図６に示すように、軸部材１に含まれるＣｒ、Ｍｏ等の元素が圧粉体２０側に拡散し、圧粉体２０に添加されているＳｉ元素、Ｐ元素が軸部材１側に拡散する。これにより、図７に示すように、軸部材１と外周部材２との間に、両者を拡散接合する拡散層３０が形成される。拡散層３０は、外周部材２側の部分３１と軸部材１側の部分３２とからなる。このうち、軸部材１側の部分３２は硬度がＨｖ３００以下のフェライト相となる。 Thereafter, in the sintering step 103, as shown in FIG. 6, elements such as Cr and Mo contained in the shaft member 1 diffuse to the green compact 20 side, and the Si element added to the green compact 20, P The element diffuses toward the shaft member 1 side. As a result, as shown in FIG. 7, a diffusion layer 30 is formed between the shaft member 1 and the outer peripheral member 2 to diffuse and bond them. The diffusion layer 30 includes a portion 31 on the outer peripheral member 2 side and a portion 32 on the shaft member 1 side. Among these, the portion 32 on the shaft member 1 side is a ferrite phase having a hardness of Hv300 or less.
この焼結工程１０３のとき、軸部材１の表層に形成されたフェライト相は元素の拡散係数が高い組織であるため、図６に示すように、圧粉体２０に添加されているＳｉが、軸部材１の圧粉体２０側の部分だけでなく軸部材１の表層にも拡散する。このＳｉはフェライト相化を促進するフェライト化元素のため、図７に示すように、さらに、フェライト相でない領域にＳｉが拡散することで、フェライト相化が促進される。これにより、フェライト相の形成範囲が拡張し、フェライト相の軸部材１の表面からの厚さが、例えば、５０μｍから２００μｍに広がる。 In the sintering step 103, since the ferrite phase formed on the surface layer of the shaft member 1 has a structure with a high element diffusion coefficient, Si added to the green compact 20 as shown in FIG. It diffuses not only in the portion of the shaft member 1 on the green compact 20 side but also in the surface layer of the shaft member 1. Since Si is a ferritic element that promotes ferrite phase formation, as shown in FIG. 7, the diffusion of Si into a region that is not a ferrite phase further promotes ferrite phase formation. Thereby, the formation range of a ferrite phase expands, and the thickness from the surface of the shaft member 1 of a ferrite phase spreads from 50 micrometers to 200 micrometers, for example.
このように、軸部材１の表面での脱炭とＳｉの拡散との相乗効果により、軸部材１の表面にフェライト相からなる軟化層３３が形成され、軸部材１の表層が軟化するものと考えられる。
（他の実施形態）
（１）第１実施形態では、軸部材１の表層に脱炭を生じさせる手段として、脱脂工程において、成形潤滑剤の分解により生成するＣＯ２とＨ２Ｏとを加熱雰囲気中に残した状態とする手段を採用したが、他の手段を採用しても良い。
Thus, due to the synergistic effect of decarburization on the surface of the shaft member 1 and diffusion of Si, a softened layer 33 made of a ferrite phase is formed on the surface of the shaft member 1, and the surface layer of the shaft member 1 is softened. Conceivable.
(Other embodiments)
(1) In the first embodiment, as a means for causing decarburization on the surface layer of the shaft member 1, a state in which CO 2 and H 2 O generated by decomposition of the molded lubricant are left in the heating atmosphere in the degreasing step. However, other means may be adopted.
例えば、第１実施形態の脱脂工程１０２を、一般的な脱脂工程と同様に、成形潤滑剤の分解によって生成するガスを加熱雰囲気から排除するように変更する。そして、この脱脂工程１０２と焼結工程１０３との間に、組み付け後の軸部材１と圧粉体とを、脱炭性雰囲気下で加熱することにより、軸部材１の表面から脱炭させる脱炭工程を追加すれば良い。このとき用いる脱炭性ガスは、ＣＯ２とＨ２Ｏの少なくとも一方のガスであれば良く、これら以外のガスであっても良い。ＣＯ２、Ｈ２Ｏ以外の脱炭性ガスとしては、Ｈ２、Ｏ２等が挙げられる。 For example, the degreasing process 102 of the first embodiment is changed so as to exclude the gas generated by the decomposition of the molding lubricant from the heating atmosphere, as in the general degreasing process. Then, between the degreasing step 102 and the sintering step 103, the assembled shaft member 1 and the green compact are heated in a decarburizing atmosphere to decarburize from the surface of the shaft member 1. What is necessary is just to add a charcoal process. The decarburizing gas used at this time may be at least one of CO 2 and H 2 O, and may be other gas. Examples of decarburizing gases other than CO 2 and H 2 O include H 2 and O 2 .
（２）第１実施形態の組み付け工程１０１では、軸部材１と、外周部材２の形状に成形された圧粉体とを用意して、圧粉体の内孔に軸部材１を嵌合して一体化したが、この組み付け工程１０１の代わりに、特許文献４に記載のように、圧粉体の成形と同時に、軸部材１と圧粉体２０とを一体化させる一体化工程を行っても良い。すなわち、金型内で軸部材１を保持した状態で、金型内の原料粉末を加圧することにより、軸部材１と圧粉体の一体化部品をインサート成形しても良い。 (2) In the assembly process 101 of the first embodiment, the shaft member 1 and the green compact molded in the shape of the outer peripheral member 2 are prepared, and the shaft member 1 is fitted into the inner hole of the green compact. However, instead of this assembling step 101, as described in Patent Document 4, an integration step of integrating the shaft member 1 and the green compact 20 at the same time as forming the green compact is performed. Also good. That is, an integrated part of the shaft member 1 and the green compact may be insert-molded by pressing the raw material powder in the mold while holding the shaft member 1 in the mold.
（３）第１実施形態では、本発明の焼結拡散接合部品の製造方法を、インジェクタのアーマチャの製造方法に適用した例を説明したが、複雑形状の焼結ギヤ部品等の他の焼結拡散接合部品の製造方法に適用することも可能である。この焼結ギヤ部品は、軸部とこの軸部の一端側に設けられたギヤ部とから構成され、軸部の形状とされた耐摩耗性材料とギヤ部の形状とされた圧粉体とを焼結拡散接合することにより得られるものである。 (3) In the first embodiment, an example in which the method for manufacturing a sintered diffusion bonding part of the present invention is applied to a method for manufacturing an armature of an injector has been described. It is also possible to apply to a method for manufacturing a diffusion bonded part. The sintered gear part is composed of a shaft portion and a gear portion provided on one end side of the shaft portion, and includes a wear-resistant material having a shape of the shaft portion and a green compact having a shape of the gear portion. Is obtained by sintering diffusion bonding.
以下、本発明の実施例について説明する。
（実施例１）
耐摩耗性材料からなる所望形状の試験片と、圧粉体を所望形状とした試験片とを焼結拡散接合により接合して焼結拡散接合部品を作製した。
Examples of the present invention will be described below.
Example 1
A specimen having a desired shape made of an abrasion-resistant material and a specimen having a green compact in a desired shape were joined by sintered diffusion bonding to produce a sintered diffusion bonded part.
具体的には、ＳＫＨ５１材からなる円柱状の耐摩耗性材料を用意した。また、組成がＳｉ：２．０ｗｔ％、Ｐ：０．３５ｗｔ％、Ｍｎ：０．２ｗｔ％、Ｓ：０．０８ｗｔ％、残部がＦｅおよび不可避不純物の金属粉末を円柱状に加圧成形した圧粉体を用意した。この圧粉体は、ワックス系の潤滑剤が圧粉体全体に対して０．５ｗｔ％添加されたものである。 Specifically, a cylindrical wear-resistant material made of SKH51 material was prepared. Further, a pressure obtained by pressure-molding a metal powder having a composition of Si: 2.0 wt%, P: 0.35 wt%, Mn: 0.2 wt%, S: 0.08 wt%, the balance being Fe and inevitable impurities in a cylindrical shape. Powder was prepared. This green compact is obtained by adding 0.5 wt% of a wax-based lubricant to the whole green compact.
そして、耐摩耗性材料の一面と圧粉体の一面とを接触させて組み付けた後、脱脂工程と焼結工程とを順に行った。脱脂工程では０．５Ｔｏｒｒの真空炉中で６３５℃にて１時間加熱した。焼結工程では０．５Ｔｏｒｒの真空炉中で１２１５℃にて１時間加熱した。 Then, after one surface of the wear-resistant material and one surface of the green compact were brought into contact with each other and assembled, a degreasing step and a sintering step were sequentially performed. In the degreasing process, heating was performed at 635 ° C. for 1 hour in a vacuum furnace of 0.5 Torr. In the sintering process, heating was performed at 1215 ° C. for 1 hour in a vacuum furnace of 0.5 Torr.
また、脱脂工程では、真空炉の内部に設置された多孔質アルミナ板の表面上に、組み付け後の耐摩耗性材料と圧粉体とを置いて加熱した。この多孔質アルミナ板は、事前処理によってＣＯ２とＨ２Ｏのガスを吸着させたものである。これにより、脱脂工程において、圧粉体中の成形潤滑剤の分解によってＣＯ２とＨ２Ｏが放出されることに加えて、多孔質アルミナ板からＣＯ２とＨ２Ｏが放出されるようにした。なお、事前処理では、真空炉の内部に多孔質アルミナ板を設置し、この多孔質アルミナ板の表面上に、この事前処理用に用意した成形潤滑剤を含む圧粉体を置いて加熱した。これにより、圧粉体中の成形潤滑剤を分解させてＣＯ２とＨ２Ｏとを圧粉体から放出させ、放出されたＣＯ２とＨ２Ｏのガスを多孔質アルミナ板に吸着させた。このように、本実施例では、ガス吸着させた多孔質アルミナ板を用いることで、成形潤滑剤の添加量を増大させたときに成形潤滑剤の分解によって加熱雰囲気中に放出されるＣＯ２とＨ２Ｏとが増大する状況と同様の状況を作り出した。 In the degreasing process, the assembled wear-resistant material and the green compact were placed on the surface of the porous alumina plate installed inside the vacuum furnace and heated. This porous alumina plate is obtained by adsorbing CO 2 and H 2 O gases by pretreatment. Accordingly, in the degreasing process, in addition to CO 2 and H 2 O is released by degradation of the molding lubricant in the green compact, as CO 2 and H 2 O is released from the porous alumina plate did. In the pretreatment, a porous alumina plate was placed inside the vacuum furnace, and a green compact containing a molding lubricant prepared for the pretreatment was placed on the surface of the porous alumina plate and heated. As a result, the molding lubricant in the green compact was decomposed to release CO 2 and H 2 O from the green compact, and the released CO 2 and H 2 O gas was adsorbed to the porous alumina plate. . Thus, in this example, by using a porous alumina plate that has been gas-adsorbed, CO 2 released into the heating atmosphere by decomposition of the molding lubricant when the amount of molding lubricant added is increased. A situation similar to that with increasing H 2 O was created.
その後、作製した焼結拡散接合部品の断面を金属顕微鏡で観察するとともに、耐摩耗性材料の表層の硬度をマイクロビッカース測定法により測定した。 Thereafter, the cross section of the produced sintered diffusion bonded part was observed with a metal microscope, and the hardness of the surface layer of the wear-resistant material was measured by a micro Vickers measurement method.
その結果、図８に示すように、耐摩耗性材料１の表層の組織が他の領域と異なっていることが確認された。また、用意した耐摩耗性材料１は、接合前の表層の硬度がＨｖ６００であったが、接合後の表層の硬度がＨｖ２００であった。これらの結果より、耐摩耗性材料１の表面に軟化層３３が形成されていることがわかる。この軟化層３３はフェライト相であると推測される。 As a result, as shown in FIG. 8, it was confirmed that the structure of the surface layer of the wear-resistant material 1 was different from other regions. Further, the prepared wear-resistant material 1 had a surface layer hardness before bonding of Hv600, but the surface layer hardness after bonding was Hv200. From these results, it can be seen that the softened layer 33 is formed on the surface of the wear-resistant material 1. The softened layer 33 is presumed to be a ferrite phase.
１ 軸部材
２ 外周部材
３ アーマチャ
１０ 電磁弁
２０ 圧粉体
２１ 成形潤滑剤
DESCRIPTION OF SYMBOLS 1 Shaft member 2 Outer peripheral member 3 Armature 10 Solenoid valve 20 Green compact 21 Molding lubricant
Claims (3)
前記耐摩耗性材料と、フェライト化元素を含有する前記圧粉体とを一体化させる一体化工程（１０１）と、
前記一体化工程後に、前記耐摩耗性材料と前記圧粉体とを脱炭性雰囲気下で加熱することにより、前記耐摩耗性材料の表層に脱炭を生じさせてフェライト相を形成する脱炭工程（１０２）と、
前記脱炭工程後に、前記耐摩耗性材料と前記圧粉体とを加熱することにより、前記圧粉体を焼結させるとともに前記耐摩耗性材料と前記圧粉体とを焼結拡散接合し、さらに、前記耐摩耗性材料の表層に前記フェライト化元素が拡散することによって前記フェライト相の形成範囲を拡張させて前記耐摩耗性材料の表面に軟化層（３３）を形成する焼結工程（１０３）と、
前記焼結工程後に、前記耐摩耗性材料の表層を切削加工する切削工程（１０４）とを有することを特徴とする焼結拡散接合部品の製造方法。 An abrasion-resistant material (1) made of carbon steel having a hardness of Hv 600 or more and having a desired shape and a green compact (20) made of an Fe-based metal containing Fe as a main component and having a desired shape are sintered. In the method of manufacturing a sintered diffusion bonded part bonded by bonded diffusion bonding,
An integration step (101) for integrating the wear-resistant material and the green compact containing a ferritic element;
After the integration step, the wear resistant material and the green compact are heated in a decarburizing atmosphere, thereby decarburizing the surface layer of the wear resistant material to form a ferrite phase. Step (102);
After the decarburization step, by heating the wear-resistant material and the green compact, the green compact is sintered and the wear-resistant material and the green compact are sintered and diffusion bonded. Further, a sintering step (103) of forming a softening layer (33) on the surface of the wear-resistant material by expanding the formation range of the ferrite phase by diffusing the ferritic element into the surface layer of the wear-resistant material. )When,
A method of manufacturing a sintered diffusion bonded part, comprising: a cutting step (104) for cutting a surface layer of the wear-resistant material after the sintering step.
前記一体化工程と前記焼結工程との間に、前記成形潤滑剤の分解温度にて加熱することにより、前記圧粉体中の前記成形潤滑剤を分解させる脱脂工程（１０２）を有し、
前記脱炭工程は、前記脱脂工程において、前記成形潤滑剤の分解によって生成したＣＯ２とＨ２Ｏとを、加熱雰囲気中に残した状態とすることであることを特徴とする請求項１に記載の焼結拡散接合部品の製造方法。 The green compact (20) contains a molding lubricant (21),
A degreasing step (102) for decomposing the molding lubricant in the green compact by heating at a decomposition temperature of the molding lubricant between the integration step and the sintering step;
The decarburizing step is a state in which CO 2 and H 2 O generated by the decomposition of the molding lubricant are left in a heated atmosphere in the degreasing step. The manufacturing method of the sintered diffusion bonding components as described.
前記軸部材の形状とされた前記耐摩耗性材料と、前記外周部材の形状とされた前記圧粉体とを一体化させることを特徴とする請求項１または２に記載の拡散接合部品の製造方法。 The sintered diffusion bonding component is an injector armature (3) having a shaft member (1) and an outer peripheral member (2) located on one end side of the shaft member,
The diffusion bonded component according to claim 1 or 2, wherein the wear-resistant material in the shape of the shaft member and the green compact in the shape of the outer peripheral member are integrated. Method.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6417804A (en) * | 1987-07-10 | 1989-01-20 | Kawasaki Steel Co | High density iron series sintered material and its production |
| JPH03232903A (en) * | 1990-02-06 | 1991-10-16 | Toyota Motor Corp | Manufacture of high carbon sintered parts |
| JPH09157706A (en) * | 1995-12-08 | 1997-06-17 | Hitachi Powdered Metals Co Ltd | Method for reforming ferrous sintered material |
| US5819154A (en) * | 1995-12-08 | 1998-10-06 | Hitachi Powdered Metal Co., Ltd. | Manufacturing process of sintered iron alloy improved in machinability, mixed powder for manufacturing, modification of iron alloy and iron alloy product |
| JP2009021490A (en) * | 2007-07-13 | 2009-01-29 | Hitachi Powdered Metals Co Ltd | Sintered soft magnetic substance and sintered movable iron core using the same, and manufacturing method of them |
| JP2009102711A (en) * | 2007-10-24 | 2009-05-14 | Denso Corp | Soft magnetic sintering material, method for producing the same, and electromagnetic structure |
-
2012
- 2012-06-08 JP JP2012130744A patent/JP5862468B2/en not_active Expired - Fee Related
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6417804A (en) * | 1987-07-10 | 1989-01-20 | Kawasaki Steel Co | High density iron series sintered material and its production |
| JPH03232903A (en) * | 1990-02-06 | 1991-10-16 | Toyota Motor Corp | Manufacture of high carbon sintered parts |
| JPH09157706A (en) * | 1995-12-08 | 1997-06-17 | Hitachi Powdered Metals Co Ltd | Method for reforming ferrous sintered material |
| US5819154A (en) * | 1995-12-08 | 1998-10-06 | Hitachi Powdered Metal Co., Ltd. | Manufacturing process of sintered iron alloy improved in machinability, mixed powder for manufacturing, modification of iron alloy and iron alloy product |
| JP2009021490A (en) * | 2007-07-13 | 2009-01-29 | Hitachi Powdered Metals Co Ltd | Sintered soft magnetic substance and sintered movable iron core using the same, and manufacturing method of them |
| JP2009102711A (en) * | 2007-10-24 | 2009-05-14 | Denso Corp | Soft magnetic sintering material, method for producing the same, and electromagnetic structure |
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