JPS5920742B2 - Ni-based alloy - Google Patents
Ni-based alloyInfo
- Publication number
- JPS5920742B2 JPS5920742B2 JP7099578A JP7099578A JPS5920742B2 JP S5920742 B2 JPS5920742 B2 JP S5920742B2 JP 7099578 A JP7099578 A JP 7099578A JP 7099578 A JP7099578 A JP 7099578A JP S5920742 B2 JPS5920742 B2 JP S5920742B2
- Authority
- JP
- Japan
- Prior art keywords
- weight
- based alloy
- curve
- present
- less
- 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
- 229910045601 alloy Inorganic materials 0.000 title claims description 24
- 239000000956 alloy Substances 0.000 title claims description 24
- 230000007797 corrosion Effects 0.000 claims description 10
- 238000005260 corrosion Methods 0.000 claims description 10
- 238000005336 cracking Methods 0.000 claims description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 20
- 150000004767 nitrides Chemical class 0.000 description 4
- 206010070834 Sensitisation Diseases 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 230000008313 sensitization Effects 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- -1 C is 0305 or less Substances 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910001055 inconels 600 Inorganic materials 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 229910001026 inconel Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Landscapes
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
- Heat Treatment Of Steel (AREA)
Description
【発明の詳細な説明】
本発明は耐食性の優れたＮｉ基合金に関し、特に加熱し
ても粒界腐食に対して鋭敏化しないＮｉ基合金に関する
。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a Ni-based alloy with excellent corrosion resistance, and particularly to a Ni-based alloy that does not become sensitive to intergranular corrosion even when heated.
従来５インコネル６００などＮｉ基合金ではＣ固溶度が
小さいことから、４００〜８００℃に短時間加熱される
だけで粒界にＣｒ炭化物を析出するため、粒界にＣｒ欠
乏層ができ、粒界腐食されやすくなる。Since Ni-based alloys such as conventional 5 Inconel 600 have low C solid solubility, Cr carbides are precipitated at grain boundaries even when heated to 400 to 800°C for a short time, resulting in the formation of Cr-depleted layers at grain boundaries. Becomes more susceptible to corrosion.
換言すれば、Ｎｉ基合金は４００〜８００℃に短時間加
熱されるだけで粒界腐食に対して鋭敏化されるという欠
点を有している。また、インコネル６００などはＴｉを
０．２重量φ程度含有しているが、このＴｉは全てＴｉ
Ｎ（Ｃ）化合物として析出してしまうため、ＴｉＣの析
出による炭化物の安定化効果が期待できない。そこで本
発明者は、鋭敏化しないＮｉ基合金を提供すべ＜Ｎｉ基
合金における各種合金元素の役割と実質とを検討したと
ころ、Ｃ量を減少させ、３有ＣとＮとを全てＴｉとＡｅ
で固定する（すなわちＴに２Ａｅの炭化物、窒化物とす
る）ことにより、結晶粒界にＣｒ炭化物やＣｒ窒化物の
析出が防止でき、耐食性が向上するという知見を得て本
発明に到達したものである。すなわち本発明はＮｉ基合
金において、Ｃを０３０５重量受以下、Ｃｒを１０〜３
０重量％ Ｆｅを５〜２０重量％、Ｔｉを２重量％以下
でＴｉ／Ｃ＋Ｔｉ／Ｎの重量比で８以上、Ａｅを１重量
％以下でＡｅ／Ｈの重量比で４以上名むことを特徴とす
る耐粒界腐食割れ性Ｎｉ基合金を要旨とするものである
。In other words, Ni-based alloys have the disadvantage that they become sensitized to intergranular corrosion even when heated to 400 to 800°C for a short time. Furthermore, Inconel 600 and the like contain Ti around 0.2 weight φ, but all of this Ti is Ti.
Since TiC is precipitated as an N(C) compound, the effect of stabilizing carbides due to TiC precipitation cannot be expected. Therefore, the present inventors investigated the role and substance of various alloying elements in Ni-based alloys in order to provide a Ni-based alloy that does not become sensitized.
The present invention was developed based on the knowledge that by fixing T with carbide or nitride of 2Ae, precipitation of Cr carbide or Cr nitride at grain boundaries can be prevented and corrosion resistance can be improved. It is. That is, in the present invention, in a Ni-based alloy, C is 0305 or less, and Cr is 10 to 3.
0 wt% Fe is 5 to 20 wt%, Ti is 2 wt% or less, Ti/C + Ti/N weight ratio is 8 or more, Ae is 1 wt% or less, Ae/H weight ratio is 4 or more. This article focuses on a Ni-based alloy that is characterized by intergranular corrosion cracking resistance.
本発明において、Ｃを０００５重量％以下としたのは、
後述の加熱処理時、本発明合金組成においてＣが完全に
固溶できる量が０２０５重量％以下であるからである。In the present invention, C is set to 0005% by weight or less because
This is because the amount of C that can be completely dissolved in solid solution in the alloy composition of the present invention during the heat treatment described below is 0.205% by weight or less.
Ｃｒは耐食性を保持させる目的で添加され、１０重量％
未満であれば耐食性が得られず１３０重量％を越えると
安定なオーステナイトが得られず長時間加熱した場合に
劣化を生じ易くなるため、その添加量は１０〜３０重量
％とした。Ｆｅは機械的性質を保持させるためと、熱膨
張％数を小さくする目的で添加され、５重量％未満であ
ると溶接割れを生じ、２０重量％を越えると熱膨張％数
が大きくなるため、その添加量は５〜２０重量％とした
。また、本発明において、Ｔｉ２Ａｅは前記したように
含有ＣとＮとを全てＴｔｔＡｅの炭化物、窒化物として
析出させるために添加される。Cr is added for the purpose of maintaining corrosion resistance, and is 10% by weight.
If it is less than 130% by weight, corrosion resistance cannot be obtained, and if it exceeds 130% by weight, stable austenite cannot be obtained and deterioration is likely to occur when heated for a long time. Therefore, the amount added is set to 10 to 30% by weight. Fe is added for the purpose of maintaining mechanical properties and reducing the thermal expansion percentage; if it is less than 5% by weight, welding cracks will occur, and if it exceeds 20% by weight, the thermal expansion percentage will increase. The amount added was 5 to 20% by weight. Further, in the present invention, Ti2Ae is added in order to precipitate all the contained C and N as carbides and nitrides of TttAe, as described above.
Ｔｉの最小必要量は原子比でＴｉ／Ｃ■ １、Ｔｉ７Ｎ
−１の合計であればよく、これを重量比で表わしてＴｉ
、／Ｃ＋Ｔｉ／Ｎ−： ８としたものであり、上限を
２重量％としたのは、これを越えると機械的性質が低下
し、もろくなるからである。Ａｅは酸素との親和力が強
《、本発明合金中で窒化物となるのは酸素と結びついた
残りであるため，原子比でＡｅ／Ｎ＝１より多目に添加
する必要があり、本発明者の検討によれば大体２倍程度
多くすればよいことが判り，最小必要量をＡｅ／Ｈの重
量比で４としたものであり、上限を１重量％としたノハ
、これを越えると機械的性質が低下し、もろ《なるから
である。本発明合金は、１０００℃以上に加熱処理（溶
体化処理を含む）すると合金中のＣが完全に固溶する。The minimum required amount of Ti is Ti/C■ 1, Ti7N in atomic ratio.
-1, and this can be expressed as a weight ratio of Ti
, /C+Ti/N-: 8, and the reason why the upper limit was set to 2% by weight is that if it exceeds this, the mechanical properties deteriorate and become brittle. Ae has a strong affinity with oxygen, and since it is the residue combined with oxygen that forms nitrides in the alloy of the present invention, it is necessary to add more than Ae/N=1 in the atomic ratio. According to the study conducted by the author, it was found that the amount should be increased by about twice as much, and the minimum required amount was set at 4 in the Ae/H weight ratio, and the upper limit was set at 1% by weight, and if this amount was exceeded, the machine This is because their physical qualities deteriorate and they become fragile. When the alloy of the present invention is heat-treated (including solution treatment) to 1000° C. or higher, C in the alloy completely dissolves in solid solution.
一度固溶したＣはその後に前記した４００〜８００℃の
加熱を施こさない限りＣｒ炭化物となって析出すること
はな（・。そこでＣを固溶させた状態で８５０〜９５０
℃の安定化処理を施せばＣは全てＴｉ炭化物となって析
出し安定化する。次に，実施例を挙げて本発明合金の効
果を具体的に説明する。実施例
Ｃ＝０．０１４重量Ｓ，ｓｉ＝０．３７重量％，Ｍｎ＝
０．３４重量係，Ｐ＝０．００２重量係，Ｓ＝０．００
ｉ重量係、Ｎｉ＝７４．００重量係、Ｃｒ＝１６．００
重量係、Ｔｉ＝０．４１重量係、Ｎ＝０．０２０５重量
％．Ａｅ：０．１０重量％、Ｆｅ＝残上記組成の本発明
Ｎｉ基合金の５朋厚熱間圧延材を１０００℃で溶体化処
理した後９００℃で安定化処理したものを２５係沸騰硝
酸（ＭＯｄｉｆｉｅｄＨｅｕｙ試験）によりＴ．Ｔ．Ｓ
曲線（加熱温度一時間一鋭敏化曲線）を作成し．第１図
に示す。Once C is dissolved in solid solution, it will not precipitate as Cr carbide unless it is heated to 400 to 800°C as described above.
If the stabilization treatment is performed at a temperature of .degree. C., all of the C becomes Ti carbide, precipitates, and stabilizes. Next, the effects of the alloy of the present invention will be specifically explained with reference to Examples. Example C=0.014 wt S, si=0.37 wt%, Mn=
0.34 weight factor, P=0.002 weight factor, S=0.00
i weight ratio, Ni = 74.00 weight ratio, Cr = 16.00
Weight factor, Ti=0.41 weight factor, N=0.0205 weight%. Ae: 0.10% by weight, Fe = remainder A 5 mm thick hot rolled material of the present invention Ni-based alloy having the above composition was solution-treated at 1000°C and then stabilized at 900°C, and then treated with 25% boiling nitric acid ( T. (Modified Heuy test). T. S
Create a curve (heating temperature per hour per sensitization curve). Shown in Figure 1.
なお，比較のために従来のＮｉ基合金としてのＩｎｃＯ
ｎｅｌ６ＯＯ（イ／ターナショナル・ニッケル・カンパ
ニー社の商標） ，ＩｎｃＯｌＯｙ８ＯＯ（インターナ
ショナルーニッケル・カンパニー社ノ商標）についても
同様にしてＴ．Ｔ．Ｓ曲線を作成し、第１図に示す。第
１図中、曲線１は本発明Ｎｉ基合金のＴ．Ｔ．Ｓ曲線、
曲線２はＩｎｃＯｎｅｌ６ＯＯのＴ．Ｔ．Ｓ曲線、曲線
３はＩｎｃＯｌＯｙ８ＯＯのＴ．Ｔ．Ｓ曲線であり、第
１図の図面の見方は第２図に示す通りである。For comparison, IncO as a conventional Ni-based alloy
T. nel6OO (trademark of International Nickel Company, Inc.) and IncOlOy8OO (trademark of International Nickel Company, Inc.) are similarly used. T. An S curve was created and shown in Figure 1. In FIG. 1, curve 1 indicates the T.I. of the Ni-based alloy of the present invention. T. S curve,
Curve 2 is IncOnel6OO's T. T. S curve, curve 3 is the T.S curve of IncOlOy8OO. T. It is an S curve, and the view of the drawing in FIG. 1 is as shown in FIG. 2.
第１図から明らかなように、ＩｎｃＯｎｅｌ６ＯＯ、Ｉ
ｎｃＯｌＯｙ８ＯＯでは４００〜８００℃の加熱により
著しい鋭敏化を呈するのに対し，本発明Ｎｉ基合金では
４００〜８００℃で１０００ｈ迄の加熱により何ら鋭敏
化を示さず．本発明Ｎｉ基合金が従来のＩｎｃＯｎｅｌ
６ＯＯ、ＩｎｃＯｌＯｙ８ＯＯに比べ優れた耐食性を有
していることが判る。As is clear from Fig. 1, IncOnel6OO, I
Whereas ncOlOy8OO shows significant sensitization when heated at 400 to 800°C, the Ni-based alloy of the present invention shows no sensitization when heated at 400 to 800°C for up to 1000 hours. The Ni-based alloy of the present invention is similar to the conventional IncOnel.
It can be seen that it has superior corrosion resistance compared to 6OO and IncOlOy8OO.
第１図は本発明Ｎｉ基合金（図中、曲線１）と従来のＮ
ｉ基合金であるＩｎｃＯｎｅｌ６ＯＯ（図中，曲線２）
、ＩｎｃＯｌＯｙ８ＯＯ（図中，曲線３）のＴ．Ｔ．Ｓ
曲線を示す図表、第２図は第１図の見方を示す説明図で
ある。Figure 1 shows the Ni-based alloy of the present invention (curve 1 in the figure) and the conventional Ni-based alloy.
IncOnel6OO, an i-based alloy (curve 2 in the figure)
, IncOlOy8OO (curve 3 in the figure). T. S
FIG. 2 is an explanatory diagram showing how FIG. 1 is viewed.
Claims (1)
ｒを１０〜３０重量％、Ｆｅを５〜２０重量％、Ｔｉを
２重量％以下でＴｉ／Ｃ＋Ｔｉ／Ｎの重量比で８以上、
Ａｌを１重量％以下でＡｌ／Ｎの重量比で４以上含むこ
とを特徴とする耐粒界腐食割れ性Ｎｉ基合金。1 In Ni-based alloy, C is 0.05% by weight or less, C
10 to 30% by weight of r, 5 to 20% by weight of Fe, 2% by weight or less of Ti, and a weight ratio of Ti/C + Ti/N of 8 or more,
A Ni-based alloy with intergranular corrosion cracking resistance characterized by containing Al at 1% by weight or less and an Al/N weight ratio of 4 or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7099578A JPS5920742B2 (en) | 1978-06-14 | 1978-06-14 | Ni-based alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7099578A JPS5920742B2 (en) | 1978-06-14 | 1978-06-14 | Ni-based alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS54162617A JPS54162617A (en) | 1979-12-24 |
| JPS5920742B2 true JPS5920742B2 (en) | 1984-05-15 |
Family
ID=13447634
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7099578A Expired JPS5920742B2 (en) | 1978-06-14 | 1978-06-14 | Ni-based alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5920742B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6274077A (en) * | 1985-09-28 | 1987-04-04 | Toshiba Corp | Susceptor for cvd device |
-
1978
- 1978-06-14 JP JP7099578A patent/JPS5920742B2/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| JPS54162617A (en) | 1979-12-24 |
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