JPH0121871B2 - - Google Patents
Info
- Publication number
- JPH0121871B2 JPH0121871B2 JP24871785A JP24871785A JPH0121871B2 JP H0121871 B2 JPH0121871 B2 JP H0121871B2 JP 24871785 A JP24871785 A JP 24871785A JP 24871785 A JP24871785 A JP 24871785A JP H0121871 B2 JPH0121871 B2 JP H0121871B2
- Authority
- JP
- Japan
- Prior art keywords
- titanium
- region
- present
- corrosion resistance
- corrosion
- 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.)
- Expired
Links
- 238000005260 corrosion Methods 0.000 claims description 48
- 230000007797 corrosion Effects 0.000 claims description 48
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 29
- 239000010936 titanium Substances 0.000 claims description 27
- 229910052719 titanium Inorganic materials 0.000 claims description 26
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 24
- 238000010438 heat treatment Methods 0.000 claims description 23
- 238000001816 cooling Methods 0.000 claims description 21
- 239000000956 alloy Substances 0.000 claims description 19
- 229910045601 alloy Inorganic materials 0.000 claims description 14
- 229910052759 nickel Inorganic materials 0.000 claims description 14
- KDLHZDBZIXYQEI-UHFFFAOYSA-N Palladium Chemical compound [Pd] KDLHZDBZIXYQEI-UHFFFAOYSA-N 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 7
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 4
- KJTLSVCANCCWHF-UHFFFAOYSA-N Ruthenium Chemical compound [Ru] KJTLSVCANCCWHF-UHFFFAOYSA-N 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 239000011733 molybdenum Substances 0.000 claims description 4
- 229910052763 palladium Inorganic materials 0.000 claims description 4
- 229910052707 ruthenium Inorganic materials 0.000 claims description 4
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 239000010937 tungsten Substances 0.000 claims description 4
- 238000005275 alloying Methods 0.000 claims description 2
- 238000000034 method Methods 0.000 description 21
- 230000000052 comparative effect Effects 0.000 description 6
- 229910004337 Ti-Ni Inorganic materials 0.000 description 5
- 229910011209 Ti—Ni Inorganic materials 0.000 description 5
- KHYBPSFKEHXSLX-UHFFFAOYSA-N iminotitanium Chemical compound [Ti]=N KHYBPSFKEHXSLX-UHFFFAOYSA-N 0.000 description 5
- 229910000990 Ni alloy Inorganic materials 0.000 description 3
- 229910003296 Ni-Mo Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910001252 Pd alloy Inorganic materials 0.000 description 2
- 229910000929 Ru alloy Inorganic materials 0.000 description 2
- 229910001080 W alloy Inorganic materials 0.000 description 2
- HZEWFHLRYVTOIW-UHFFFAOYSA-N [Ti].[Ni] Chemical compound [Ti].[Ni] HZEWFHLRYVTOIW-UHFFFAOYSA-N 0.000 description 2
- 238000010587 phase diagram Methods 0.000 description 2
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Description
目 的
この発明は、ニツケルを含有するチタン基合金
を熱処理により耐食性を向上させるチタン基合金
材の製造方法に関するものである。
従来技術
純チタンは、耐食性が優れているので従来から
種々の化学プラントや、電極、熱交換器等に広く
使用されているが、昨今のよりきびしい腐食環境
下での使用のためには、純チタンの耐食性だけで
は充分でなく、より一層の耐食性に富む材料の開
発が望まれている。
このような中で、純チタンにニツケルを添加し
た耐食性チタン合金Ti−Ni合金（特公昭46−
21086）やTi−Ni−Mo合金（特願昭50−37435）
の開発がなされた。
しかしながら、このようなニツケルを含有した
チタン基合金においても比較的強い腐食環境下で
はしばしば腐食の問題が発生し、さらに、耐食性
を向上させる必要が生じてきた。
発明の構成
本発明者は、上記実情に鑑み鋭意研究を行つた
結果、本発明を見い出すに到つた。すなわち本発
明は、
(1) 重量％でニツケル0.1％〜７％残部チタン及
び不可避的不純物からなるチタン基合金を、α
＋β領域又はβ領域に加熱し、しかるのち50
℃／分以上の速さで冷却することを特徴とする
耐食性に優れたチタン基合金材の製造方法。
(2) 重量％でニツケル0.1％〜７％及び、ルテニ
ウム0.005％〜2.0％、パラジウム0.005％〜2.0
％、モリブデン0.01％〜1.0％、タングステン
0.005％〜0.5％の合金元素の群から選択した１
種又は２種以上を含有し、残部チタン及び不可
避的不純物からなるチタン基合金を、α＋β領
域又はβ領域に加熱し、しかる後50℃／分以上
の速さで冷却することを特徴とする耐食性に優
れたチタン基合金材の製造方法に関するもので
ある。
通常、チタンにニツケルを添加した場合、第１
図のTi−Ni状態図に示すように、室温付近にお
いては、ニツケルはほとんどチタンに固溶せず
Ti2Niの形でα−チタンの粒界に析出する。
従来のニツケルを含有したチタン基合金は、こ
のような状態にて耐食性を向上させるものであつ
た。しかるに、本発明方法にしたがい、チタン−
ニツケル合金をα＋β又はβ領域に加熱し、その
後急冷を行い、ニツケルをα−チタン中に多く固
溶させることによつて、チタン−ニツケル系合金
の耐食性が著しく向上することを見い出したので
ある。
前記ニツケル含有量の下限を0.1重量％とした
のは、これより少ないとニツケル含有の効果がな
く、又、上限を７重量％としたのは、これよりニ
ツケル含有量が多いと加工性が悪くなり実質的に
製造がむずかしくなるためである。
また、副成分であるルテニウム、パラジウム、
モリブデン、タングステンについても、その下限
より少ない含有量では、耐食性を向上させるのに
ほとんど効果がないためである。上限について
は、ルテニウム、パラジウムは、それより多く添
加しても耐食性を向上させる効果があまり上昇し
なくなり、コスト高となるためであり、又、モリ
ブデン、タングステンを上限より多く添加するこ
とは、著しく製造が困難となるためである。
次に、本発明を具体的な実施例に基づいて説明
する。
実施例
チタンに、ニツケル0.1重量％〜７重量％を含
有するTi−Ni合金、Ti−Ni−Mo合金、Ti−Ni
−Ru合金、Ti−Ni−Pd合金、Ti−Ni−Ｗ合金、
について、本発明の実施例と比較例を第１表〜第
５表に示す。加熱温度は700℃（α領域）、800℃
（α＋β領域）、1000℃（β領域）の３種類とし、
冷却速度及び腐食試験は第１表〜第５表に示す条
件下にて行つた。
第１表に、Ti−Ni合金の腐食試験結果を示す。
※印が本発明方法による例であり、他は比較例を
示す。
加熱温度は700℃（α領域）においては、冷却
速度を変化させても腐食速度はほとんどかわら
ず、又、本発明方法により熱処理を行つたものに
比べ著しく腐食速度が大きい。
加熱温度800℃（α＋β領域）、及び1000℃（β
領域）とした場合、冷却速度が10℃／分の場合
と、本発明方法である50℃／分、200℃／分、
1000℃／分では、明らかに腐食速度が異なつてお
り、本発明方法が耐食性の向上に寄与しているこ
とがわかる。
このように、加熱温度がα＋β領域もしくはβ
領域であり、しかも、冷却速度が50℃／分以上の
２条件が整つて初めて耐食性が向上することがわ
かる。
第２表に、Ti−Ni−Mo合金の腐食試験結果を
示す。※印が本発明方法による例であり、他は比
較例を示す。
加熱温度700℃（α領域）においては、冷却速
度を変化させても腐食速度はほとんどかわらず、
又、本発明方法により熱処理を行つたものに比べ
著しく腐食速度が大きい。
加熱温度800℃（α＋β領域）、及び1000℃（β
領域）とした場合、冷却速度が10℃／分の場合
と、本発明方法である50℃／分、200℃／分、
1000℃／分では、明らかに腐食速度が異なつてお
り、本発明方法が耐食性の向上に寄与しているこ
とがわかる。
このように、加熱温度がα＋β領域もしくはβ
領域であり、しかも、冷却速度が50℃／分以上の
２条件が整つて初めて耐食性が向上することがわ
かる。
第３表に、Ti−Ni−Ru合金の腐食試験結果を
示す。※印が本発明方法による例であり、他は比
較例を示す。
加熱温度700℃（α領域）においては、冷却速
度を変化させても腐食速度はほとんどかわらず、
又、本発明方法により熱処理を行つたものに比べ
著しく腐食速度が大きい。
加熱温度800℃（α＋β領域）、及び1000℃（β
領域）とした場合、冷却速度が10℃／分の場合
と、本発明方法である50℃／分、200℃／分、
1000℃／分では、明らかに腐食速度が異なつてお
り、本発明方法が耐食性の向上に寄与しているこ
とがわかる。
このように、加熱温度がα＋β領域もしくはβ
領域であり、しかも、冷却速度が50℃／分以上の
２条件が整つて初めて耐食性が向上することがわ
かる。
第４表に、Ti−Ni−Pd合金の腐食試験結果を
示す。※印が本発明方法による例であり、他は比
較例を示す。
加熱温度700℃（α領域）においては、冷却速
度を変化させても腐食速度はほとんどかわらず、
又、本発明方法により熱処理を行つたものに比べ
著しく腐食速度が大きい。
加熱温度800℃（α＋β領域）、及び1000℃（β
領域）とした場合、冷却速度が10℃／分の場合
と、本発明方法である50℃／分、200℃／分、
1000℃／分では、明らかに腐食速度が異なつてお
り、本発明方法が耐食性の向上に寄与しているこ
とがわかる。
このように、加熱温度がα＋β領域もしくはβ
領域であり、しかも、冷却速度が50℃／分以上の
２条件が整つて初めて耐食性が向上することがわ
かる。
第５表に、Ti−Ni−Ｗ合金の腐食試験結果を
示す。※印が本発明方法による例であり、他は比
較例を示す。
加熱温度700℃（α領域）においては、冷却速
度を変化させても腐食速度はほとんどかわらず、
又、本発明方法により熱処理を行つたものに比べ
著しく腐食速度が大きい。
加熱温度800℃（α＋β領域）、及び1000℃（β
領域）とした場合、冷却速度が10℃／分の場合
と、本発明方法である50℃／分、200℃／分、
1000℃／分では、明らかに腐食速度が異なつてお
り、本発明方法が耐食性の向上に寄与しているこ
とがわかる。
このように、加熱温度がα＋β領域もしくはβ
領域であり、しかも、冷却速度が50℃／分以上の
２条件が整つて初めて耐食性が向上することがわ
かる。
以上の実施例より、本発明の熱処理を行なうこ
とにより、耐食性が著しく向上することがわか
る。
Purpose This invention relates to a method for producing a titanium-based alloy material, which improves the corrosion resistance of a titanium-based alloy containing nickel by heat treatment. Prior Art Pure titanium has excellent corrosion resistance and has been widely used in various chemical plants, electrodes, heat exchangers, etc., but in recent years pure titanium has been used in more severe corrosive environments. The corrosion resistance of titanium alone is not sufficient, and the development of materials with even higher corrosion resistance is desired. Under these circumstances, a corrosion-resistant titanium alloy Ti-Ni alloy (Special Public Interest Publication 1976-
21086) and Ti-Ni-Mo alloy (patent application 1984-37435)
was developed. However, even in such titanium-based alloys containing nickel, corrosion problems often occur in relatively strong corrosive environments, and furthermore, it has become necessary to improve the corrosion resistance. Structure of the Invention The present inventor conducted extensive research in view of the above circumstances, and as a result, discovered the present invention. That is, the present invention provides: (1) a titanium-based alloy consisting of nickel, 0.1% to 7% by weight, the balance titanium, and unavoidable impurities;
Heating to +β region or β region, then 50
A method for producing a titanium-based alloy material with excellent corrosion resistance, which is characterized by cooling at a rate of at least ℃/min. (2) Nickel 0.1% to 7%, Ruthenium 0.005% to 2.0%, Palladium 0.005% to 2.0% by weight
%, Molybdenum 0.01%~1.0%, Tungsten
1 selected from the group of alloying elements from 0.005% to 0.5%
Corrosion resistance characterized by heating a titanium-based alloy containing one or more species, the remainder being titanium and unavoidable impurities, to the α+β region or β region, and then cooling at a rate of 50°C/min or more. The present invention relates to a method for producing a titanium-based alloy material with excellent properties. Usually, when nickel is added to titanium, the first
As shown in the Ti-Ni phase diagram in the figure, nickel hardly dissolves in titanium at around room temperature.
It precipitates at the grain boundaries of α-titanium in the form of Ti 2 Ni. Conventional titanium-based alloys containing nickel have improved corrosion resistance under such conditions. However, according to the method of the present invention, titanium-
It has been discovered that the corrosion resistance of titanium-nickel alloys can be significantly improved by heating the nickel alloy to the α+β or β region and then rapidly cooling it to form a solid solution of a large amount of nickel in the α-titanium. The reason why the lower limit of the nickel content was set to 0.1% by weight is that if it is less than this, the effect of nickel content is not achieved, and the reason why the upper limit is set to 7% by weight is that if the nickel content is higher than this, the processability is poor. This is because manufacturing becomes substantially difficult. In addition, the subcomponents ruthenium, palladium,
This is because when the content of molybdenum and tungsten is less than the lower limit, there is little effect on improving corrosion resistance. Regarding the upper limit, the effect of improving corrosion resistance of ruthenium and palladium will not increase much even if added in larger amounts, resulting in higher costs.Additionally, adding more than the upper limit of molybdenum and tungsten will significantly increase the corrosion resistance. This is because manufacturing becomes difficult. Next, the present invention will be explained based on specific examples. Examples Ti-Ni alloy containing 0.1% to 7% by weight of nickel in titanium, Ti-Ni-Mo alloy, Ti-Ni
-Ru alloy, Ti-Ni-Pd alloy, Ti-Ni-W alloy,
Examples and comparative examples of the present invention are shown in Tables 1 to 5. Heating temperature is 700℃ (α region), 800℃
(α+β region), 1000℃ (β region),
Cooling rate and corrosion tests were conducted under the conditions shown in Tables 1 to 5. Table 1 shows the corrosion test results for Ti-Ni alloys.
The * mark indicates an example according to the method of the present invention, and the others indicate comparative examples. At a heating temperature of 700° C. (α region), the corrosion rate hardly changes even if the cooling rate is changed, and the corrosion rate is significantly higher than that of those heat-treated by the method of the present invention. Heating temperature 800℃ (α + β region) and 1000℃ (β
range), the cooling rate is 10°C/min, and the method of the present invention is 50°C/min, 200°C/min,
At 1000° C./min, the corrosion rates are clearly different, indicating that the method of the present invention contributes to improving corrosion resistance. In this way, the heating temperature is in the α+β region or β
It can be seen that corrosion resistance improves only when two conditions are met: a cooling rate of 50°C/min or more. Table 2 shows the corrosion test results for Ti-Ni-Mo alloys. The * mark indicates an example according to the method of the present invention, and the others indicate comparative examples. At a heating temperature of 700℃ (α region), the corrosion rate hardly changes even if the cooling rate is changed.
Furthermore, the corrosion rate is significantly higher than that of those heat-treated by the method of the present invention. Heating temperature 800℃ (α + β region) and 1000℃ (β
range), the cooling rate is 10°C/min, and the method of the present invention is 50°C/min, 200°C/min,
At 1000° C./min, the corrosion rates are clearly different, indicating that the method of the present invention contributes to improving corrosion resistance. In this way, the heating temperature is in the α+β region or β
It can be seen that corrosion resistance improves only when two conditions are met: a cooling rate of 50°C/min or more. Table 3 shows the corrosion test results for the Ti-Ni-Ru alloy. The * mark indicates an example according to the method of the present invention, and the others indicate comparative examples. At a heating temperature of 700℃ (α region), the corrosion rate hardly changes even if the cooling rate is changed.
Furthermore, the corrosion rate is significantly higher than that of those heat-treated by the method of the present invention. Heating temperature 800℃ (α + β region) and 1000℃ (β
range), the cooling rate is 10°C/min, and the method of the present invention is 50°C/min, 200°C/min,
At 1000° C./min, the corrosion rates are clearly different, indicating that the method of the present invention contributes to improving corrosion resistance. In this way, the heating temperature is in the α+β region or β
It can be seen that corrosion resistance improves only when two conditions are met: a cooling rate of 50°C/min or more. Table 4 shows the corrosion test results for Ti-Ni-Pd alloys. The * mark indicates an example according to the method of the present invention, and the others indicate comparative examples. At a heating temperature of 700℃ (α region), the corrosion rate hardly changes even if the cooling rate is changed.
Furthermore, the corrosion rate is significantly higher than that of those heat-treated by the method of the present invention. Heating temperature 800℃ (α + β region) and 1000℃ (β
range), the cooling rate is 10°C/min, and the method of the present invention is 50°C/min, 200°C/min,
At 1000° C./min, the corrosion rates are clearly different, indicating that the method of the present invention contributes to improving corrosion resistance. In this way, the heating temperature is in the α+β region or β
It can be seen that corrosion resistance improves only when two conditions are met: a cooling rate of 50°C/min or more. Table 5 shows the corrosion test results for the Ti-Ni-W alloy. The * mark indicates an example according to the method of the present invention, and the others indicate comparative examples. At a heating temperature of 700℃ (α region), the corrosion rate hardly changes even if the cooling rate is changed.
Furthermore, the corrosion rate is significantly higher than that of those heat-treated by the method of the present invention. Heating temperature 800℃ (α + β region) and 1000℃ (β
range), the cooling rate is 10°C/min, and the method of the present invention is 50°C/min, 200°C/min,
At 1000° C./min, the corrosion rates are clearly different, indicating that the method of the present invention contributes to improving corrosion resistance. In this way, the heating temperature is in the α+β region or β
It can be seen that corrosion resistance improves only when two conditions are met: a cooling rate of 50°C/min or more. From the above examples, it can be seen that corrosion resistance is significantly improved by performing the heat treatment of the present invention.
【表】【table】
【表】【table】
【表】【table】
【表】【table】
【表】【table】
【表】【table】
第１図はチタン−ニツケル合金の状態図であ
る。
FIG. 1 is a phase diagram of a titanium-nickel alloy.
Claims (1)
び不可避的不純物からなるチタン基合金を、α＋
β領域又はβ領域に加熱し、しかるのち50℃／分
以上の速さで冷却することを特徴とする耐食性に
優れたチタン基合金材の製造方法。 ２ 重量％でニツケル0.1〜７％、及びルテニウ
ム0.005％〜2.0％、パラジウム0.005％〜2.0％、
モリブデン0.01％〜1.0％、タングステン0.005％
〜0.5％の合金元素の群から選択した１種又は２
種以上を含有し、残部チタン及び不可避的不純物
からなるチタン基合金を、α＋β領域又はβ領域
に加熱し、しかる後50℃／分以上の速さで冷却す
ることを特徴とする耐食性に優れたチタン基合金
材の製造方法。[Claims] 1% by weight of a titanium-based alloy consisting of nickel, 0.1% to 7%, the balance titanium, and unavoidable impurities, α+
A method for producing a titanium-based alloy material with excellent corrosion resistance, which comprises heating to the β region or β region, and then cooling at a rate of 50° C./min or more. 2 nickel 0.1-7%, ruthenium 0.005%-2.0%, palladium 0.005%-2.0%,
Molybdenum 0.01%~1.0%, tungsten 0.005%
~0.5% of one or two selected from the group of alloying elements
A titanium-based alloy with excellent corrosion resistance, which is characterized by heating a titanium-based alloy containing more than 50% titanium and the remainder consisting of titanium and unavoidable impurities to the α+β region or β region, and then cooling it at a rate of 50°C/min or more. A method for producing a titanium-based alloy material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24871785A JPS62109955A (en) | 1985-11-08 | 1985-11-08 | Manufacture of titanium-base alloy material excellent in corrosion resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24871785A JPS62109955A (en) | 1985-11-08 | 1985-11-08 | Manufacture of titanium-base alloy material excellent in corrosion resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62109955A JPS62109955A (en) | 1987-05-21 |
| JPH0121871B2 true JPH0121871B2 (en) | 1989-04-24 |
Family
ID=17182291
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP24871785A Granted JPS62109955A (en) | 1985-11-08 | 1985-11-08 | Manufacture of titanium-base alloy material excellent in corrosion resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62109955A (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63219557A (en) * | 1987-03-09 | 1988-09-13 | Nippon Mining Co Ltd | Production of titanium based alloy material having excellent corrosion resistance and press moldability |
| JPH0267322A (en) * | 1988-09-02 | 1990-03-07 | Tosoh Corp | Equipment for manufacturing polyarylene sulfide |
| CN118345410A (en) * | 2024-05-09 | 2024-07-16 | 鞍钢集团北京研究院有限公司 | A titanium alloy bipolar plate with high pitting potential and low resistivity and a method for preparing the same |
-
1985
- 1985-11-08 JP JP24871785A patent/JPS62109955A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS62109955A (en) | 1987-05-21 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EXPY | Cancellation because of completion of term |