JPS61246333A - Manufacture of high density ti sintered alloy - Google Patents
Manufacture of high density ti sintered alloyInfo
- Publication number
- JPS61246333A JPS61246333A JP60085501A JP8550185A JPS61246333A JP S61246333 A JPS61246333 A JP S61246333A JP 60085501 A JP60085501 A JP 60085501A JP 8550185 A JP8550185 A JP 8550185A JP S61246333 A JPS61246333 A JP S61246333A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- sintered
- density
- sintered alloy
- alloy
- 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.)
- Granted
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 18
- 239000000956 alloy Substances 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 239000000843 powder Substances 0.000 claims abstract description 53
- 238000005275 alloying Methods 0.000 claims abstract description 10
- 238000005245 sintering Methods 0.000 claims abstract description 8
- 229910001069 Ti alloy Inorganic materials 0.000 claims abstract description 5
- 238000010298 pulverizing process Methods 0.000 claims abstract description 5
- 239000011812 mixed powder Substances 0.000 claims description 9
- 239000000654 additive Substances 0.000 claims description 7
- 230000000996 additive effect Effects 0.000 claims description 7
- 238000002156 mixing Methods 0.000 claims description 6
- 238000005054 agglomeration Methods 0.000 claims 1
- 230000002776 aggregation Effects 0.000 claims 1
- 239000003795 chemical substances by application Substances 0.000 claims 1
- 239000007788 liquid Substances 0.000 claims 1
- 230000003449 preventive effect Effects 0.000 claims 1
- 238000000034 method Methods 0.000 abstract description 22
- 239000000203 mixture Substances 0.000 abstract description 7
- 239000002245 particle Substances 0.000 abstract description 7
- 238000007796 conventional method Methods 0.000 abstract description 5
- 238000009792 diffusion process Methods 0.000 abstract description 4
- 238000004904 shortening Methods 0.000 abstract description 2
- 238000010586 diagram Methods 0.000 description 7
- 238000005242 forging Methods 0.000 description 5
- 239000002994 raw material Substances 0.000 description 5
- 238000009694 cold isostatic pressing Methods 0.000 description 3
- 238000005056 compaction Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- BDERNNFJNOPAEC-UHFFFAOYSA-N propan-1-ol Chemical compound CCCO BDERNNFJNOPAEC-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000002457 bidirectional effect Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 239000002923 metal particle Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000010025 steaming Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
Ｌ１１立皿ユニ１
本発明は、高密度Ｔｉ焼結合金の製造方法に関するもの
である。DETAILED DESCRIPTION OF THE INVENTION L11 Standing plate unit 1 The present invention relates to a method for producing a high-density Ti sintered alloy.
よ の口 従来、Ｔｉ焼結合金は、下記の方法で製造されている。yo's mouth Conventionally, Ti sintered alloys have been manufactured by the following method.
（１）要素粉末法（第１図参照）：
■；粉末と合金化用添加粉末とを混合しく第■工程）、
これを金型に装入して圧粉成形しく第■工程）、この圧
粉体を真空中、またはアルゴン・ガス雰囲気中で焼結す
る（第■工程）。そして、焼結体を鍛造（第■工程）後
、または鍛造を行うことなく、仕上げ加工（第Ｖ工程）
して成品を得る。(1) Elemental powder method (see Figure 1): ■; Mixing the powder and the additive powder for alloying (Step ■),
This is charged into a mold and compacted into powder (step 1), and the compact is sintered in a vacuum or in an argon gas atmosphere (step 2). Then, after forging the sintered body (Step ■) or without forging, finishing processing (Step V) is performed.
and obtain a finished product.
なお、第■工程では、冷間静水圧プレス成形法（ＣＩＰ
）により圧粉体を得る場合もある。In addition, in the second step, cold isostatic pressing method (CIP) is used.
) may also be used to obtain a green compact.
この要素粉末法では、■素材粉末が、未だ目標合金組成
のものでなく、従って製造経費が低置である、■素材粉
末の混合比を変えて、組成の異なる各種の合金を得るこ
とができる、等の利点があるが、圧粉成形圧を８ｔｏｎ
／ｃｉにした場合の成品の密度が最大９８％であり、成
品の疲労強度が不足する不都合がある。In this elemental powder method, 1) the raw material powder does not yet have the target alloy composition, so the manufacturing cost is low; 2) it is possible to obtain various alloys with different compositions by changing the mixing ratio of the raw material powders , etc., but the compacting pressure is 8 tons.
/ci, the density of the product is at most 98%, and there is a disadvantage that the fatigue strength of the product is insufficient.
（２）合金粉末法（第２図参照）：
目標組成に調整された均一合金粉末を、押型内に装入し
て焼結温度で圧搾しくＨＩＰ ：第Ｉ工程）、得られた
焼結体を仕上げ加工して（第■工程）成品を得る。(2) Alloy powder method (see Figure 2): The uniform alloy powder adjusted to the target composition is charged into a mold and compressed at the sintering temperature.HIP: Step I), the obtained sintered body Finish processing (Step ■) to obtain a finished product.
この合金粉末法では、■焼結体の密度を１００χにする
ことができ、■それ故、事後の鍛造加工を行う必要がな
い、■冷間圧粉法では成形困難な粉末でも容易に成形し
得る、等の利点があるが、■素材である均一合金粉末の
製造費が高価である、■押型として耐熱鋼型、炭素型が
使用され、その都度使い捨てされるため、製造費が高価
になる、■押型と共に加熱、圧搾されるため、多量生産
方式の採用が困難である、等の不都合がある。With this alloy powder method, ■ it is possible to make the density of the sintered body 100χ, ■ therefore there is no need for subsequent forging, ■ it is possible to easily mold powders that are difficult to mold using the cold compaction method. However, the manufacturing cost of the homogeneous alloy powder that is the raw material is high; ■ The manufacturing cost is high because heat-resistant steel molds and carbon molds are used as the stamping molds, and they are discarded each time. , ■Since it is heated and pressed together with the pressing mold, it is difficult to adopt a mass production method.
ｐ ′ だ の び
本発明の目的は、多量生産方式に適する簡易な方法で高
密度の焼結体を得る点にある。An object of the present invention is to obtain a high-density sintered body by a simple method suitable for mass production.
この目的は、Ｔｉ、またはＴｉ合金粉末と合金化用添加
粉末とを所定割合で混合してなる混合粉末を、機械的粉
砕手段にて処即し、該粉砕処理した混合粉末を圧粉成形
した後、これを焼結させることによって達成される。The purpose of this was to process a mixed powder obtained by mixing Ti or Ti alloy powder and an additive powder for alloying in a predetermined ratio with a mechanical pulverizer, and then compact the pulverized mixed powder. This is then achieved by sintering it.
ＴｉまたはＴｉ合金粉末１と、合金化用添加粉末２を混
合して（第３図参照）、更に粉砕処理を行うと、両種の
粉末が更に微細化されて粉末内部に歪が発生するととも
に相互に密にからみ合った結合粒子３が生じ（第４図参
照。但し、１ａ、２ａはそれぞれ粉末１．２の変形後の
状態を示す）、接触面積の増大と、焼結時における拡散
距離の短縮が達成され、結合粒子３ないし粒子１ａ、２
ａは、従来法による粉末に比して、言わば活性化された
状態になって、処理粉末を通常圧で圧粉成形後、真空焼
結を行った場合でも９９％以上の焼結密度を得ることが
できる。When Ti or Ti alloy powder 1 and additive powder for alloying 2 are mixed (see Figure 3) and further pulverized, both types of powder are further refined and strain is generated inside the powder. Bonded particles 3 are formed that are tightly entangled with each other (see Figure 4. However, 1a and 2a each show the state after deformation of the powder 1.2), which increases the contact area and the diffusion distance during sintering. A shortening of the bonded particles 3 to particles 1a, 2 is achieved.
A is in an activated state compared to the powder produced by the conventional method, and even when the treated powder is compacted under normal pressure and then vacuum sintered, a sintered density of 99% or more is obtained. be able to.
また、融点の差が大きな合金元素を、単一成分粉末とし
て混合し、従来方法により圧粉成形後、焼結した場合に
は、低融点金属の液化によって該金属粒子部分が空孔に
なり易り１．その現象を避けるために母合金化した粉末
を使用する必要があったが、本発明方法によれば、単一
成分粉末を使用しても空孔が生じ難く、高い焼結密度を
得ることが可能である。Furthermore, when alloying elements with large differences in melting point are mixed as a single component powder and sintered after compaction using a conventional method, the metal particles tend to become pores due to the liquefaction of the low melting point metal. ri1. In order to avoid this phenomenon, it was necessary to use mother-alloyed powder, but according to the method of the present invention, even if a single-component powder is used, voids are unlikely to occur and high sintered density can be obtained. It is possible.
加えて、本発明方法によれば、粉末混合後の粉砕処理の
程度（活性化の程度）を変化させることにより焼結体の
結晶粒度を調整することができる。In addition, according to the method of the present invention, the grain size of the sintered body can be adjusted by changing the degree of pulverization treatment (degree of activation) after powder mixing.
支ＪＬＪＩ
（１）二種類の粉末、すなわち、その組成が、Ｔｉ９９
、２ｗｔ％、Ｏ（Ｍ素） ０．２ｖｔ％、ＦＢ ０．
０２４ｗｔ％、Ｃ４） ０．１３ｗｔ％であって、表１
に示す粒度分布のＴｉ粉末と、その組成が、ＡＮ ６０
ｗｔ％、Ｖ ４０ｗｔ％で、粒度が２５０メツシユ以下
の合金化用添加粉末とを用意した（以下、第５図参照）
。Branch JLJI (1) Two types of powder, that is, the composition is Ti99
, 2wt%, O (M element) 0.2vt%, FB 0.
024wt%, C4) 0.13wt%, Table 1
Ti powder with the particle size distribution shown in and its composition is AN 60
wt%, V 40wt%, and an alloying additive powder with a particle size of 250 mesh or less was prepared (see Figure 5 below).
.
（２）第工工程二次に、Ｔｉ粉末と合金化用添加粉末を
、重量比９：１の混合比で、Ｖ型ブレンダーをもって１
０分間混合した。(2) Second process: Ti powder and additive powder for alloying are mixed at a weight ratio of 9:1, and mixed with a V-type blender.
Mixed for 0 minutes.
（３）第■工程：混合された粉末に、３ｃｍ３／粉末１
００Ｑｒのプロピル・アルコールを凝集剤として添表
１
加して、振動ミル（１４５０ｒｐｏ＋ ）を用い、室温
にて、０．５〜１２時間の粉砕処理を行った。粉砕処理
は、これをボールミルで行うこともできるが、振動ミル
に比して長時間を要する不都合がある。なお、凝集剤と
してはへブタンを使用することもできるが、凝集剤の添
加口は、これを１〜５００１１’ ／粉末１００ｇｒに
するのが好ましい。その理由は、添加量が１ＣＩＩ３／
粉末１０００ｒ未満であると、粉末が凝集し、高密度な
焼結体が得られないばかりか、圧粉成形性に劣るからで
あり、添加量が５０国３／粉末１００ｇｒを越えると、
添加量に比して効果が少なく、く、次の圧粉成形工程に
先立って必要な凝集剤の減圧除去処理に長時間を要し、
量産性が損なわれるからである。(3) Step ■: Add 3cm3/1 powder to the mixed powder.
Attach 00Qr of propyl alcohol as a flocculant.
In addition, pulverization treatment was performed for 0.5 to 12 hours at room temperature using a vibration mill (1450 rpo+). The pulverization process can also be carried out using a ball mill, but this has the disadvantage of requiring a longer time than a vibrating mill. Although hebutane can be used as the flocculant, it is preferable to add the flocculant at an amount of 1 to 50011'/100 gr of powder. The reason is that the amount added is 1CII3/
If the amount of powder is less than 1000g, the powder will aggregate and not only will it not be possible to obtain a high-density sintered body, but the compactability will be poor.If the amount added exceeds 50gr/100gr of powder,
The effect is small compared to the amount added, and it takes a long time to remove the flocculant under reduced pressure, which is necessary before the next compaction process.
This is because mass productivity is impaired.
（４）第■工程：粉砕処理された混合粉末を金型に装入
し、圧粉成形した。この工程では、冷静水圧プレス成形
法（ＣＩＰ）を採用することもできる。(4) Step (1): The pulverized mixed powder was charged into a mold and compacted. In this step, cold hydraulic press molding (CIP) can also be employed.
（５）第■工程：圧粉体を、真空度１０″４〜１０′６
履Ｈ（１゜温度１２５０℃、処理時間４時間なる条件で
焼結処理した。なお、処理雰囲気は、不活性ガス雰囲気
でも良く、温度、処理時間は、それぞれ１１００〜１４
００℃、１〜４時間の範囲で条件選択することができる
。その限定理由は、１１００℃未満では、十分な拡散が
行われず、１４００℃を越えると、均一組成の焼結体が
得られないからであり、また１時間未満では、十分な拡
散が行われず、４時間を越えたとしても高密度化は蒸捏
進行せず、量産性が損なわれるからである。(5) Step ■: The green compact is vacuumed at a vacuum level of 10″4 to 10′6.
The sintering process was carried out under the conditions of 1° temperature of 1250°C and a processing time of 4 hours.The processing atmosphere may be an inert gas atmosphere, and the temperature and processing time were 1100 to 1400°C, respectively.
Conditions can be selected within the range of 00°C and 1 to 4 hours. The reason for this limitation is that if the temperature is less than 1,100°C, sufficient diffusion will not take place, if the temperature exceeds 1,400°C, a sintered body with a uniform composition will not be obtained, and if the temperature is less than 1 hour, sufficient diffusion will not take place. This is because even if the time exceeds 4 hours, densification will not proceed through steaming and mass productivity will be impaired.
（６）第Ｖ工程：焼結体を鍛造後、または鍛造を行うこ
となく、仕上げ加工（第■工程）を行って成品を得る。(6) Step V: After forging the sintered body, or without forging, finish processing (step (Ⅰ)) is performed to obtain a finished product.
斯かる製造工程によれば、密度９９％以上の成品を得る
ことができ、第■工程のみを省略して他の条件を本実施
例と同一にして得た成品の密度９６．５％に比して十分
高密度であり、大幅な強度向上を期待し得る（第６図参
照）。According to this manufacturing process, it is possible to obtain a product with a density of 99% or more, which is compared to the density of 96.5% of the product obtained by omitting only step (2) and keeping the other conditions the same as in this example. It has a sufficiently high density, and a significant improvement in strength can be expected (see Fig. 6).
なお、第７図は前者（本実施例による成品）の組織を示
す写真（倍率１００）であり、第８図は後者（従来法に
よる成品）の組織を示す写真（倍率１００）である。後
者は、前者と比して空孔（黒い斑点）が多く、粒度も大
きいこと杯判る。Note that FIG. 7 is a photograph (magnification: 100) showing the structure of the former (product according to this example), and FIG. 8 is a photograph (magnification: 100) showing the structure of the latter (product according to the conventional method). It is clear that the latter has more pores (black spots) and larger grain size than the former.
ｌ■Ｌ皇１
以上の説明から明らかな様に、本発明では、Ｔｉ、また
はＴｉ合金粉末と、合金化用添加粉末とを所定割合で混
合してなる混合粉末を、機械的粉砕手段にて処理し、粉
砕処理した混合粉砕を圧粉成形した後、これを焼結させ
ることとしたため、量産に適する簡単な方法で高密度の
焼結合金を得ることができる。As is clear from the above description, in the present invention, a mixed powder obtained by mixing Ti or Ti alloy powder and an additive powder for alloying in a predetermined ratio is pulverized by mechanical crushing means. Since the treated and pulverized mixed pulverized powder is compacted and then sintered, a high-density sintered alloy can be obtained by a simple method suitable for mass production.
第１図、第２図はそれぞれ公知に係る焼結金属の製造工
程図、第３図は本発明方法を実施するために二種類の素
材粉末を混合した状態を示す図、第４図はその混合粉末
を粉砕処理した後の粉末を示す図、第５図は本発明方法
によるＴｉ焼結合金の製造工程図、第６図は両振引張り
、圧縮疲労試験（Ｎ＝１０７）によるＴｉ焼結合金の密
度と応力の関係を示すグラフ、第７図は本発明方法で製
造した丁１焼結合金の組織図（１００倍）、第８図は従
来方法で製造したＴｉ焼結合金の組織図（１００倍）で
ある。
第１図
ＩＩ［ＩＩＩ
第２図
Ｉ ｎ
第３図
第４図
ｎ
第、５・図
ｎＩＮ
第６図Figures 1 and 2 are diagrams of a known manufacturing process for sintered metal, Figure 3 is a diagram showing a state in which two types of raw material powder are mixed to carry out the method of the present invention, and Figure 4 is a diagram showing the state in which two types of raw material powder are mixed to carry out the method of the present invention. A diagram showing the powder after the mixed powder has been pulverized. Figure 5 is a process diagram for producing a Ti sintered alloy according to the method of the present invention. Figure 6 is a Ti sintered composite obtained by bidirectional tension and compression fatigue tests (N=107). A graph showing the relationship between gold density and stress. Figure 7 is a microstructure diagram (100x magnification) of a Ti sintered alloy produced by the method of the present invention. Figure 8 is a diagram of a Ti sintered alloy produced by a conventional method. (100 times). Figure 1 II [III Figure 2 I n Figure 3 Figure 4 n Figure 5, Figure n IN Figure 6
Claims (4)
所定割合で混合して成る混合粉末を、機械的粉砕手段に
て処理し、該粉砕処理した混合粉末を圧粉成形した後、
これを焼結させることを特徴とする高密度Ｔｉ焼結合金
の製造方法。(1) After processing a mixed powder obtained by mixing Ti or Ti alloy powder and an additive powder for alloying in a predetermined ratio with a mechanical pulverizing means, and compacting the pulverized mixed powder,
A method for producing a high-density Ti sintered alloy, which comprises sintering this.
を特徴とする特許請求の範囲第１項に記載された高密度
Ｔｉ焼結合金の製造方法。(2) The method for producing a high-density Ti sintered alloy according to claim 1, characterized in that a vibration mill is used as the mechanical crushing means.
合粉末中に１〜５０ｃｍ＾３／粉末１００ｇｒの液体状
の凝集防止剤を添加することを特徴とする特許請求の範
囲第１項または第２項に記載された高密度Ｔｉ焼結合金
の製造方法。(3) When performing the treatment by the mechanical crushing means, a liquid agglomeration preventive agent is added to the mixed powder in an amount of 1 to 50 cm^3/100 gr of powder. A method for producing a high-density Ti sintered alloy as described in item 2.
〜４時間なる条件で、前記焼結を行うことを特徴とする
特許請求の範囲第１項、第２項、または第３項に記載さ
れた高密度Ｔｉ焼結合金の製造方法。(4) In vacuum, temperature 1100-1400℃, processing time 1
The method for producing a high-density Ti sintered alloy according to claim 1, 2, or 3, wherein the sintering is performed under conditions of 4 hours to 4 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60085501A JPS61246333A (en) | 1985-04-23 | 1985-04-23 | Manufacture of high density ti sintered alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60085501A JPS61246333A (en) | 1985-04-23 | 1985-04-23 | Manufacture of high density ti sintered alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61246333A true JPS61246333A (en) | 1986-11-01 |
| JPH0440414B2 JPH0440414B2 (en) | 1992-07-02 |
Family
ID=13860678
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60085501A Granted JPS61246333A (en) | 1985-04-23 | 1985-04-23 | Manufacture of high density ti sintered alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61246333A (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5160608A (en) * | 1974-09-26 | 1976-05-26 | Jei Haaueru Chaaruzu | |
| JPS56123301A (en) * | 1979-11-26 | 1981-09-28 | Gould Inc | High density sintered powder alloy and its manufacture |
| JPS61159539A (en) * | 1984-12-29 | 1986-07-19 | Toshiba Corp | Manufacture of shape memory alloy |
-
1985
- 1985-04-23 JP JP60085501A patent/JPS61246333A/en active Granted
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5160608A (en) * | 1974-09-26 | 1976-05-26 | Jei Haaueru Chaaruzu | |
| JPS56123301A (en) * | 1979-11-26 | 1981-09-28 | Gould Inc | High density sintered powder alloy and its manufacture |
| JPS61159539A (en) * | 1984-12-29 | 1986-07-19 | Toshiba Corp | Manufacture of shape memory alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0440414B2 (en) | 1992-07-02 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EXPY | Cancellation because of completion of term |