JPH03193801A - Sintering additive powder for intermetallic compound and sintering method thereof - Google Patents
Sintering additive powder for intermetallic compound and sintering method thereofInfo
- Publication number
- JPH03193801A JPH03193801A JP1335783A JP33578389A JPH03193801A JP H03193801 A JPH03193801 A JP H03193801A JP 1335783 A JP1335783 A JP 1335783A JP 33578389 A JP33578389 A JP 33578389A JP H03193801 A JPH03193801 A JP H03193801A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- sintering
- intermetallic compound
- alloy powder
- sintered
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000000843 powder Substances 0.000 title claims abstract description 48
- 238000005245 sintering Methods 0.000 title claims abstract description 25
- 238000000034 method Methods 0.000 title claims abstract description 21
- 229910000765 intermetallic Inorganic materials 0.000 title claims abstract description 18
- 239000000654 additive Substances 0.000 title abstract description 5
- 230000000996 additive effect Effects 0.000 title abstract description 4
- 229910000521 B alloy Inorganic materials 0.000 claims abstract description 7
- 239000002245 particle Substances 0.000 claims abstract description 7
- 229910018507 Al—Ni Inorganic materials 0.000 claims abstract description 6
- 229910018575 Al—Ti Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000000465 moulding Methods 0.000 claims description 13
- 239000000203 mixture Substances 0.000 abstract description 7
- 238000002156 mixing Methods 0.000 abstract description 4
- 238000009703 powder rolling Methods 0.000 abstract description 3
- 229910052796 boron Inorganic materials 0.000 abstract description 2
- 238000002347 injection Methods 0.000 abstract 1
- 239000007924 injection Substances 0.000 abstract 1
- 239000011812 mixed powder Substances 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 19
- 239000000956 alloy Substances 0.000 description 19
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 7
- 239000000047 product Substances 0.000 description 6
- 239000007791 liquid phase Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000001746 injection moulding Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- 229910000943 NiAl Inorganic materials 0.000 description 1
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 description 1
- 229910021330 Ti3Al Inorganic materials 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- QDWJUBJKEHXSMT-UHFFFAOYSA-N boranylidynenickel Chemical compound [Ni]#B QDWJUBJKEHXSMT-UHFFFAOYSA-N 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000009770 conventional sintering Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000003779 heat-resistant material Substances 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は金属間化合物からなる耐熱材料、耐摩耗材料と
して用いられるＡｌ−Ｔｉ 、Ａｌ−Ｎｌ系の金属間
化合物焼結材料に関するものである。[Detailed Description of the Invention] [Field of Industrial Application] The present invention relates to a heat-resistant material made of an intermetallic compound and a sintered material of an Al-Ti or Al-Nl-based intermetallic compound used as a wear-resistant material. .
Ａｌ−ＴｉおよびＡｌ−Ｎｉ系の金属間化合物焼結製品
を製造するにはＡＣＴｉ、Ｎｉの粉末を目的とする組成
に合せて混合した後、圧縮成形し焼結工程に付す。この
ようにして製造される製品の相対密度は７０〜８０％で
強度も溶製材にくらべるとかなり低い。To produce Al-Ti and Al-Ni based intermetallic compound sintered products, ACTi and Ni powders are mixed to a desired composition, then compression molded and subjected to a sintering process. The relative density of the product manufactured in this way is 70 to 80%, and the strength is also considerably lower than that of ingot lumber.
焼結製品の密度を上げるための方法として反応焼結法が
あるが、反応の制御がむずかしく、５％程度の気孔が残
りやすい。更に密度を高める方法として熱間静水圧成形
法がある。しかしこの方法は複雑で高価な装置を用いる
ことおよび最終製品の形状が限定され、しかも最終製品
を直接製造することができない。このように従来法には
それぞれ一長一短があり満足しうる特性の焼結晶を得る
ことが難しかった。Reactive sintering is a method for increasing the density of sintered products, but it is difficult to control the reaction and tends to leave around 5% of pores. Hot isostatic pressing is a method for further increasing the density. However, this method requires the use of complicated and expensive equipment, the shape of the final product is limited, and furthermore, the final product cannot be manufactured directly. As described above, each of the conventional methods has advantages and disadvantages, and it has been difficult to obtain sintered crystals with satisfactory characteristics.
こうした事情に着目し、高価で複雑な工程をへることな
く、高密度で強度が高くかつ寸法安定性のすぐれた焼結
体を得るための種々の検討を重ねた。Focusing on these circumstances, we conducted various studies to obtain a sintered body with high density, high strength, and excellent dimensional stability without having to go through expensive and complicated processes.
焼結法のなかで液相を利用した活性化焼結方法は、
少量の添加物によって成形圧力、成形方法によらず焼結
体の密度を向上させるのに有効である。そこでマトリッ
クスのＡ １−ＴｉおよびＡｌ−Ｎｉ系粉末に溶解度が
大きく、かつぬれ性がよく、しかも少量でその目的を達
っするものを種々検討した結果、Ａｌ１−Ｔｉ、および
Ａｊ！−Ｎｉ系粉末の焼結に際して有効な添加用合金粉
末と新たな焼結添加用合金粉末を加える焼結法を見出し
本発明を完成した。Among the sintering methods, the activated sintering method that utilizes a liquid phase is effective in improving the density of sintered bodies using a small amount of additives, regardless of the molding pressure or molding method. Therefore, we investigated various materials that had high solubility in matrix A1-Ti and Al-Ni powders, had good wettability, and achieved the purpose with a small amount, and we found Al1-Ti and Aj! The present invention was completed by discovering a sintering method for adding an alloy powder for addition and a new alloy powder for addition to sintering that is effective in sintering Ni-based powder.
本発明に係る焼結添加用合金粉末はＡｊ！ −Ｔｉおよ
びＡｊ！−Ｎｉ系の金属間化合物粉末と配合して焼結製
品を製造するための添加用粉末であってＢを３．５〜１
８重量％、残部がＮｉおよび不可避不純物からなり、平
均粒径が３０１！ｍ以下のＮｉ −８合金粉末であり、
焼結法は前言己Ｎｉ −８合金粉末をＡｊ！−Ｔｉおよ
びＡｌ−Ｎｉ系の金属間化合物粉末に０．５重量％〜８
重量％添加して混合し、成形後、その加熱温度が１１０
０℃〜１３５０℃でその時間が１０〜１２０分間加熱す
ることを特徴とする焼結方法である。The alloy powder for sintering addition according to the present invention is Aj! -Ti and Aj! - Additive powder for producing sintered products by blending with Ni-based intermetallic compound powder, containing 3.5 to 1 B
8% by weight, the remainder consisting of Ni and unavoidable impurities, and the average particle size is 301! m or less Ni-8 alloy powder,
The sintering method uses Ni-8 alloy powder as described above. -0.5% by weight to 8% by weight of Ti and Al-Ni intermetallic compound powders
After adding weight% and mixing, after molding, the heating temperature is 110
This sintering method is characterized by heating at 0°C to 1350°C for 10 to 120 minutes.
本発明に係るＮｉ −８合金粉末はその融点が９９０℃
〜１２８０℃の範囲にある。本発明のＮｉ −Ｂ合金は
真空溶解炉にて純Ｎｉ板、ホウ化ニッケル、ボロンの塊
などを原料にして溶解した後鋳造して鋳片を製造する。The Ni-8 alloy powder according to the present invention has a melting point of 990°C.
~1280°C. The Ni-B alloy of the present invention is produced by melting pure Ni plates, nickel boride, boron ingots, etc. as raw materials in a vacuum melting furnace, and then casting to produce slabs.
その鋳片をショークラッシャー等の粗粉砕機で粗粉砕し
、その後、ボールミル、遊星ミル等で微粉砕して３０−
以下の粉末を製造する。The slab is coarsely crushed using a coarse crusher such as a show crusher, and then finely crushed using a ball mill, planetary mill, etc.
The following powders are manufactured.
この合金粉末をＡｌ−Ｔ１およびＡｊ！−Ｎｉ系の金属
間化合物粉末に添加して混合した後成形を行なう。This alloy powder is used as Al-T1 and Aj! - After being added to the Ni-based intermetallic compound powder and mixed, molding is performed.
成形法としてはプレス成形や射出成形でもよく、また粉
末圧延法でもよく、成形後、加熱して焼結する。The molding method may be press molding or injection molding, or may be a powder rolling method, and after molding, it is heated and sintered.
本発明合金粉末は焼結工程の加熱時に溶融して液相とな
り、金属間化合物粉末間のすき間に毛管現象によって浸
透して化合物の密度を上げるばかりでなく、金属間化合
物粉末と反応して液相量を増加させ焼結を促進する。The alloy powder of the present invention melts into a liquid phase during heating during the sintering process, and not only penetrates into the gaps between the intermetallic compound powders by capillary action to increase the density of the compound, but also reacts with the intermetallic compound powders to form a liquid phase. Increases phase amount and promotes sintering.
本発明のＮｉ −８合金粉末においてＢ量を３．５〜１
８重量％に限定したのは３．５％未満および１８％超で
は融点が１３００℃以上になるためであり、好ましい範
囲は４〜１５％である。In the Ni-8 alloy powder of the present invention, the amount of B is 3.5 to 1.
The reason why it is limited to 8% by weight is because if it is less than 3.5% or more than 18%, the melting point will be 1300°C or higher, and the preferable range is 4 to 15%.
また本発明において上記のごと＜Ｎｉ −Ｂ合金組成を
設定するとともに合金粉末の粒度を３０−以下とする必
要がある。粒度が３０Ｊａをこえると金属間化合物粉末
との混合が不均一となり、焼結状態が不均質となって焼
結体の密度および強度が低下するとともに寸法変化のば
らつきが大きくなる。In addition, in the present invention, it is necessary to set the Ni-B alloy composition as described above and to set the particle size of the alloy powder to 30- or less. If the particle size exceeds 30 Ja, the mixture with the intermetallic compound powder becomes non-uniform, the sintered state becomes non-uniform, the density and strength of the sintered body decrease, and the variation in dimensional changes increases.
本発明においては上記の如＜Ｎｉ −Ｂ合金組成の設定
および粒度の設定とともに、金属間化合物粉末への添加
量と焼結条件を設定する必要がある。In the present invention, in addition to setting the Ni-B alloy composition and particle size as described above, it is necessary to set the amount added to the intermetallic compound powder and the sintering conditions.
金属間化合物粉末への添加量は０．５〜８重量％で、０
．５重量％未満では液相量が少なく焼結はほとんど促進
されない。The amount added to the intermetallic compound powder is 0.5 to 8% by weight, and 0.
．． If it is less than 5% by weight, the amount of liquid phase is small and sintering is hardly promoted.
また添加量が８重量％超ではその焼結促進効果は飽和し
てしまうことおよび焼結体が溶融して形がくずれてしま
うためである。Furthermore, if the amount added exceeds 8% by weight, the sintering promoting effect will be saturated and the sintered body will melt and lose its shape.
焼結温度を１１００℃〜１３５０℃に限定した理由は１
１００℃未満では液相の発生が少なく効果がないためで
あり、１３５０℃超では焼結体の組織が粗大化して特性
が劣化することによる。The reason for limiting the sintering temperature to 1100°C to 1350°C is 1.
This is because if it is less than 100°C, the generation of liquid phase is small and there is no effect, and if it is more than 1350°C, the structure of the sintered body becomes coarse and its properties deteriorate.
従来の方法によれば金属間化合物粉末を５〜１０ｔ ／
ｃｕｔの成形圧で成形し、１３００℃で焼結しても密
度は９０％以下であり、成形方向による収縮率の差が大
きく現われる。本発明によれば１〜３ｔｏｎ／ｃＩＩ！
のような低い成形圧でも相対密度を９８％以上に上げる
ことができ金型の摩耗を最小限にすることができる。さ
らに粉末圧延法のような低い成形圧力の成形法を利用す
ることができ板状の製品の製造も可能である。According to the conventional method, the amount of intermetallic compound powder is 5 to 10 tons/
Even when molded at a molding pressure of 1,300° C. and sintered at 1300° C., the density is less than 90%, and there is a large difference in shrinkage rate depending on the molding direction. According to the present invention, 1 to 3 tons/cII!
Even with such a low molding pressure, the relative density can be increased to over 98%, and mold wear can be minimized. Furthermore, it is possible to use a molding method with low molding pressure, such as a powder rolling method, and it is also possible to manufacture a plate-shaped product.
従来、射出成形法では１０−以下の特殊な粉末しか密度
が上がらないためその利用は制限されていたが、本発明
によれば通常の大きさの粉末が利用できるためこの分野
の大きな発展が期待できる。Conventionally, the injection molding method only increased the density of special powders of 10- or less, so its use was limited, but with the present invention, powders of normal sizes can be used, so major developments in this field are expected. can.
上述のように本発明は経済的にも、焼結晶の特性上から
も画期的なものである。As mentioned above, the present invention is revolutionary both economically and in terms of the characteristics of the fired crystal.
つぎに、この発明を実施例により具体的に説明する。 Next, the present invention will be specifically explained with reference to Examples.
金属間化合物粉末としてＴｉＡ Ｒ、Ｔｉ３Ａｌ、Ｎｉ
３ｉ。TiAR, Ti3Al, Ni as intermetallic compound powder
3i.
ＮｉＡｌ粉を用い、これにインゴットを粉砕して作成し
たＮｉ −８合金粉末を第１表に示す添加量で加えてボ
ールミルにて１時間混合した後、３ ｔｏｎ／ｃｄの圧
力でタブレットを作成した。またＮｉ −８合金粉末を
添加混合した粉末に有機バインダーを加えて射出成形を
行ない板状の試験片を作成した。さらにＮｉ −８合金
粉末を添加混合した粉末を圧延ロールにより粉末圧延を
行なって板状の試験片を作成した。これらの試験片を第
１表に示す焼結条件で焼結し、焼結体の密度、硬度を測
定した。これらの測定結果を第１表に示した。また比較
の目的でＮｉ −８合金粉末を添加しない材料およびＮ
ｉ−８合金粉末の組成、焼結温度の影響を調べた比較例
も第１表に示した。Using NiAl powder, Ni-8 alloy powder prepared by crushing an ingot was added in the amount shown in Table 1, mixed in a ball mill for 1 hour, and then tablets were created at a pressure of 3 ton/cd. . Further, an organic binder was added to a powder obtained by adding and mixing Ni-8 alloy powder, and injection molding was performed to prepare a plate-shaped test piece. Furthermore, the powder to which Ni-8 alloy powder was added and mixed was powder-rolled using rolling rolls to prepare a plate-shaped test piece. These test pieces were sintered under the sintering conditions shown in Table 1, and the density and hardness of the sintered bodies were measured. The results of these measurements are shown in Table 1. For comparison purposes, materials without Ni-8 alloy powder and N
Table 1 also shows comparative examples in which the influence of the composition of the i-8 alloy powder and the sintering temperature was investigated.
本発明法１〜４に示したようにＮｉ −８合金粉末の添
加によって焼結体の相対密度は９８％以上になり高い硬
度が得られる。Ｎｉ −８合金粉末を添加しない場合は
比較例１〜４に示したように相対密度は９０％以下で硬
度も低い。またＮｉ −８合金粉末の組成が本発明の範
囲の３．５％未満では比較例５のように添加の効果が現
われず、さらに焼結温度が１１００℃未満では比較例６
のように添加の効果が現われない。As shown in Methods 1 to 4 of the present invention, by adding the Ni-8 alloy powder, the relative density of the sintered body becomes 98% or more and high hardness can be obtained. When Ni-8 alloy powder is not added, as shown in Comparative Examples 1 to 4, the relative density is 90% or less and the hardness is low. Furthermore, when the composition of Ni-8 alloy powder is less than 3.5% of the range of the present invention, the effect of addition does not appear as in Comparative Example 5, and furthermore, when the sintering temperature is less than 1100°C, Comparative Example 6
The effect of the addition does not appear.
以下余日
〔発明の効果〕
以上説明したように、本発明によって製造される焼結製
品は従来の材料に比べて、密度、硬度ともにすぐれた特
性を示す。[Effects of the Invention] As explained above, the sintered product manufactured by the present invention exhibits superior properties in both density and hardness compared to conventional materials.
また、本発明では少量の合金粉末の添加によって従来の
焼結方法よりもより経済的かつ迅速にすぐれた特性の焼
結晶を得ることができることである。Further, in the present invention, by adding a small amount of alloy powder, a sintered crystal with excellent properties can be obtained more economically and quickly than in the conventional sintering method.
Claims (2)
避不純物からなり、平均粒径が３０μｍ以下であること
を特徴とする金属間化合物焼結添加用Ｎｉ−Ｂ合金粉末
。(1) A Ni-B alloy powder for use in sintering and adding intermetallic compounds, comprising 3.5 to 18% by weight of B, the balance being Ni and unavoidable impurities, and having an average particle size of 30 μm or less.
避不純物からなり、平均粒径が３０μｍ以下であるＮｉ
−Ｂ合金粉末をＡｌ−ＴｉおよびＡｌ−Ｎｉ系の金属間
化合物粉末に重量で０．５〜８％添加して混合し、成形
後、１１００℃〜１３５０℃の温度範囲で加熱すること
を特徴とする焼結方法。(2) Ni consisting of 3.5 to 18% by weight of B, the balance being Ni and unavoidable impurities, and having an average particle size of 30 μm or less
-B alloy powder is added to Al-Ti and Al-Ni intermetallic compound powder in an amount of 0.5 to 8% by weight, mixed, and after molding, heated in a temperature range of 1100°C to 1350°C. sintering method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1335783A JPH03193801A (en) | 1989-12-25 | 1989-12-25 | Sintering additive powder for intermetallic compound and sintering method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1335783A JPH03193801A (en) | 1989-12-25 | 1989-12-25 | Sintering additive powder for intermetallic compound and sintering method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03193801A true JPH03193801A (en) | 1991-08-23 |
Family
ID=18292398
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1335783A Pending JPH03193801A (en) | 1989-12-25 | 1989-12-25 | Sintering additive powder for intermetallic compound and sintering method thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03193801A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007139194A1 (en) * | 2006-05-31 | 2007-12-06 | Kyocera Corporation | Composite material, method for manufacturing the composite material, composition used for the composite material and blade using the composite material |
| JP2013133500A (en) * | 2011-12-27 | 2013-07-08 | Tdk Corp | Sintered electrode, multilayer electronic component, internal electrode paste, method of producing sintered electrode, and method of producing multilayer electronic component |
| CN103498074A (en) * | 2013-10-21 | 2014-01-08 | 武汉理工大学 | Novel Ni3Al-based self-lubricating composite material and preparing method thereof |
| WO2017175499A1 (en) * | 2016-04-05 | 2017-10-12 | 三菱重工航空エンジン株式会社 | SINTERED BODY OF TiAl INTERMETALLIC COMPOUND AND METHOD FOR PRODUCING SINTERED BODY OF TiAl INTERMETALLIC COMPOUND |
-
1989
- 1989-12-25 JP JP1335783A patent/JPH03193801A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007139194A1 (en) * | 2006-05-31 | 2007-12-06 | Kyocera Corporation | Composite material, method for manufacturing the composite material, composition used for the composite material and blade using the composite material |
| JP2013133500A (en) * | 2011-12-27 | 2013-07-08 | Tdk Corp | Sintered electrode, multilayer electronic component, internal electrode paste, method of producing sintered electrode, and method of producing multilayer electronic component |
| CN103498074A (en) * | 2013-10-21 | 2014-01-08 | 武汉理工大学 | Novel Ni3Al-based self-lubricating composite material and preparing method thereof |
| WO2017175499A1 (en) * | 2016-04-05 | 2017-10-12 | 三菱重工航空エンジン株式会社 | SINTERED BODY OF TiAl INTERMETALLIC COMPOUND AND METHOD FOR PRODUCING SINTERED BODY OF TiAl INTERMETALLIC COMPOUND |
| JP2017186609A (en) * | 2016-04-05 | 2017-10-12 | 三菱重工航空エンジン株式会社 | TiAl-BASED INTERMETALLIC COMPOUND SINTERED BODY AND MANUFACTURING METHOD OF TiAl-BASED INTERMETALLIC COMPOUND SINTERED BODY |
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