JPH02247365A - Plastic working method for b-containing ni-base heat resisting alloy - Google Patents
Plastic working method for b-containing ni-base heat resisting alloyInfo
- Publication number
- JPH02247365A JPH02247365A JP6886889A JP6886889A JPH02247365A JP H02247365 A JPH02247365 A JP H02247365A JP 6886889 A JP6886889 A JP 6886889A JP 6886889 A JP6886889 A JP 6886889A JP H02247365 A JPH02247365 A JP H02247365A
- Authority
- JP
- Japan
- Prior art keywords
- working
- hot
- temperature
- heat treatment
- resistant 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
- 239000000956 alloy Substances 0.000 title claims abstract description 49
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 49
- 238000000034 method Methods 0.000 title claims abstract description 14
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 238000000137 annealing Methods 0.000 claims abstract description 14
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 14
- 229910052796 boron Inorganic materials 0.000 claims abstract description 11
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- 238000005554 pickling Methods 0.000 claims abstract description 8
- 238000005242 forging Methods 0.000 claims abstract description 5
- 238000005098 hot rolling Methods 0.000 claims abstract description 3
- 238000005482 strain hardening Methods 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 9
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 238000005266 casting Methods 0.000 claims description 3
- 239000000203 mixture Substances 0.000 description 10
- 238000010622 cold drawing Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 239000012535 impurity Substances 0.000 description 7
- 229910052715 tantalum Inorganic materials 0.000 description 4
- 239000000470 constituent Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 150000001247 metal acetylides Chemical group 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 229910052721 tungsten Inorganic materials 0.000 description 3
- -1 C: 0.04~0.25% Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 229910052735 hafnium Inorganic materials 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、Ｂ含有Ｎ１基耐熱合金からなる加工素材を
、その加工素材に含有するボロン含有量を減少させるこ
となく塑性加工する方法に関するものであり、さらに詳
細には、
Ｃ：０．０４〜０．２５％
Ｃｒ：２０．０〜２５．０％
Ｍｏ：８．０〜１０．０％
Ｂ ：口、００１〜０．１％
を必須成分組成として含有するＢ含有Ｎｌ基耐熱合金か
ら、直径：８１以下の細線材、板厚：５ｍｍ以下の薄板
、肉厚：５ｍｍ以下の薄肉管等をＢ含有量を減少させる
ことなく大気中で塑性加工により製造する方法に関する
ものである。[Detailed Description of the Invention] [Industrial Application Field] This invention relates to a method for plastic working a processed material made of a B-containing N1-based heat-resistant alloy without reducing the boron content contained in the processed material. In more detail, C: 0.04-0.25% Cr: 20.0-25.0% Mo: 8.0-10.0% B: 001-0.1% are required. From a B-containing Nl-based heat-resistant alloy that contains B as a component composition, fine wire rods with a diameter of 81 or less, thin plates with a thickness of 5 mm or less, thin-walled tubes with a wall thickness of 5 mm or less, etc. can be produced in the atmosphere without reducing the B content. The present invention relates to a manufacturing method using plastic working.
上記、
Ｃ：０．０４〜０．２５％
Ｃｒ：２０．ｏ 〜２５．０％
Ｍｏ：８．Ｏ〜１０．０％
Ｂ ：Ｏ，ＯＯ１〜０．１％
を必須成分組成として含有するＢ含有Ｎｌ基耐熱合金と
して、
Ｃ：０．０４〜０．２５％、 Ｃｒ：２０．０
〜２５，０％。Above, C: 0.04-0.25% Cr: 20. o ~25.0% Mo:8. O~10.0% B: O, OO1~0.1% as an essential component composition, as a B-containing Nl-based heat-resistant alloy, C: 0.04~0.25%, Cr: 20.0
~25,0%.
Ｍｏ＋８．０〜ｔｏ、ｏ％、 Ｂ ：０．０
０１〜０．１％を必須成分組成として含有し、さらに、
Ｗ ：５．０％以下、 Ｍ ｎ ： １ 、５
％以下。Mo+8.0~to, o%, B: 0.0
01 to 0.1% as an essential component composition, and further,
W: 5.0% or less, Mn: 1, 5
%below.
ｓ １：１．０％以下、 Ｆ ｅ：２０．０
％以下。s 1: 1.0% or less, Fe: 20.0
%below.
１！：１．５％以下、 Ｔ １：１．０％以
下。1! : 1.5% or less, T 1: 1.0% or less.
Ｃｏ：２０％以下、 Ｃｕ：０．５％以下
。Co: 20% or less, Cu: 0.5% or less.
のうち１種または２種以上を含有し、さらに必要に応じ
て、
Ｚ ｒ：０．０５％以下、 Ｃａ：０．０２％以下、希
土類金属：０．０２％以下のうち１種または２種以上、
Ｎｂ、Ｔａ、Ｈｆ’のうち１種または２種以上を合計で
５％以下、
を含有し、残り二Ｎ１および不可避不純物からなる組成
（以上、重量％）を有するＮ１基耐熱合金が知られてお
り、このＮｉ基耐熱合金は高温強度と耐酸化性に優れ、
上記Ｎ１基耐熱合金に含有されるＢは、特に高温クリー
プ特性向上に寄与することも知られている。これらＢ含
有Ｎｉ基耐熱合金のうち代表的なものは、特公昭５５−
９９４０号公報に記載されている
Ｃ ：０．０４〜０゜２５％。Contains one or more of the following, and further contains one or two of Zr: 0.05% or less, Ca: 0.02% or less, and rare earth metals: 0.02% or less. that's all,
An N1-based heat-resistant alloy is known which has a composition (weight %) containing one or more of Nb, Ta, and Hf' in a total of 5% or less, and the remainder consisting of two N1 and unavoidable impurities. This Ni-based heat-resistant alloy has excellent high-temperature strength and oxidation resistance,
It is also known that B contained in the N1-based heat-resistant alloy particularly contributes to improving high-temperature creep properties. Among these B-containing Ni-based heat-resistant alloys, representative ones are
C described in Japanese Patent No. 9940: 0.04 to 0°25%.
Ｆ ｅ：ｌＢ、ｏ 〜２０．０％。Fe: 1B, o ~ 20.0%.
Ｗ ：０．２〜１，０％。W: 0.2-1.0%.
Ｓ １：０．０５〜０．５％。S1: 0.05-0.5%.
Ａｇ：０．１％以下。Ag: 0.1% or less.
Ｃｏ：ｏ、６％以下。Co: o, 6% or less.
Ｚ ｒ：０．０５％以下、 Ｃａ：０．０２％以下、
希土類金属＝０．０２％以下のうち１種または２種以上
を含有し、残り：Ｎ１および不可避不純物からなる組成
（以上、重量％）を有するＮｉ基耐熱合金、ＡＭＳ規格
５５３ＢＨの
Ｃ：０．０５〜０．１５％、 Ｃｒ：２０．５
〜２３．０％。Zr: 0.05% or less, Ca: 0.02% or less,
A Ni-based heat-resistant alloy containing one or more of rare earth metals = 0.02% or less, the remainder: N1, and unavoidable impurities (weight %), AMS standard 553BH C: 0. 05-0.15%, Cr:20.5
~23.0%.
Ｆ ｅ： １７．０〜２０．０％、 Ｍｏ：８．
０〜１０．０％。Fe: 17.0-20.0%, Mo: 8.
0-10.0%.
Ｃｒ：２０．０〜２５．０％。Cr: 20.0-25.0%.
Ｍｏ：８．０〜１０．０％。Mo: 8.0-10.0%.
Ｍｎ：０．４〜１．５ ％。Mn: 0.4-1.5%.
Ｂ ：０．０２％以下。B: 0.02% or less.
Ｔｉ：０．０２％以下。Ti: 0.02% or less.
Ｗ ：０．２〜１．０％、 Ｍｎ：１％以下。W: 0.2 to 1.0%, Mn: 1% or less.
Ｓｌ：１％以下、 Ｂ ：０．０１％以下
。Sl: 1% or less, B: 0.01% or less.
Ａｌ１：０．５％以下、Ｔｉ：０．１５％以下２Ｃｏ：
０．５〜２．５％、 Ｃｕ：０．５％以下。Al1: 0.5% or less, Ti: 0.15% or less 2Co:
0.5 to 2.5%, Cu: 0.5% or less.
Ｐ二０．０４％以下、 ｓ ：０．０３％以
下。P2: 0.04% or less, s: 0.03% or less.
を含有し、残り二ＮＩおよび不可避不純物からなる組成
（以上、重量％）を有するＮｉ基耐熱合金、Ｃ：ｏ、ｏ
ｓ％、 Ｃｒ：２１％。Ni-based heat-resistant alloy having a composition (the above, weight %) consisting of the remaining 2 NI and unavoidable impurities, C: o, o
s%, Cr: 21%.
Ｍｏ：９．０％、 Ｗ：３％。Mo: 9.0%, W: 3%.
Ｂ ：０．００３％、 Ａ、１７：０．３
〜１．５％。B: 0.003%, A, 17:0.3
~1.5%.
Ｔｉ：０．１〜１．０％、 Ｃｏ：４．７〜９
．４％。Ti: 0.1-1.0%, Co: 4.7-9
．． 4%.
を含有し、残り二Ｎｌおよび不可避不純物からなる組成
（以上、重量％）を有するＮ１基耐熱合金、Ｃ：０．０
８％、 Ｃｒ：２１％。N1-based heat-resistant alloy having a composition (the above, weight %) consisting of the remaining two Nl and unavoidable impurities, C: 0.0
8%, Cr: 21%.
Ｍ ｏ ： ９ 、０％、 Ｗ ：０．０
０３％。Mo: 9, 0%, W: 0.0
03%.
Ａｌ１：０．５％、 Ｔｉ：０．３％。Al1: 0.5%, Ti: 0.3%.
Ｃｏ： １２％。Co: 12%.
を含有し、残り二ＮＩおよび不可避不純物からなる組成
（以上、重量％）を有するＮ１基耐熱合金、などのＮ１
基耐熱合金が知られている。N1-base heat-resistant alloys, such as N1-based heat-resistant alloys, having a composition (by weight %) consisting of the remaining 2 NI and unavoidable impurities.
Basic heat-resistant alloys are known.
これらＢ含有Ｎｌ２Ｚ耐熱合金のうちでも特に原子炉の
熱交換器などに用いられる特公昭５５−９９４０号公報
記載のＢ含有Ｎ１基耐熱合金線材を加工するには、次の
ようにされていた。Among these B-containing Nl2Z heat-resistant alloys, the B-containing N1-based heat-resistant alloy wire described in Japanese Patent Publication No. 55-9940, which is particularly used for heat exchangers of nuclear reactors, was processed as follows.
まず通常の真空誘導溶解炉により溶解し鋳造して作製さ
れた所望の成分組成を有するＢ含有Ｎ１基耐熱合金イン
ゴットを、温度： １１８０℃で分塊鍛造してビレット
を作製し、このビレットを、温度：１１５０℃３０分保
持後水冷の中間焼鈍したのち、酸洗し、冷間引抜して丸
棒とし、さらに温度： １１５０℃３０分保持後水冷の
中間焼鈍−酸洗−冷間引抜を２回以上繰返して線材とし
、最終的に、温度： １１８０℃１時間保持後水冷の中
間焼鈍−酸洗−冷間引抜し、さらに必要に応じて温度：
１１８０℃で最終熱処理して細線材を製造していた。First, a B-containing N1-based heat-resistant alloy ingot having a desired composition, which was produced by melting and casting in a normal vacuum induction melting furnace, was bloomed at a temperature of 1180°C to produce a billet, and this billet was Temperature: 1150℃ held for 30 minutes, water-cooled intermediate annealing, pickled, cold drawn to form a round bar, temperature: 1150℃ held for 30 minutes, water-cooled intermediate annealed - pickled - cold drawn 2 This is repeated several times or more to obtain a wire rod, and finally, after being held at a temperature of 1180°C for 1 hour, it is subjected to water-cooled intermediate annealing, pickling, and cold drawing.
Fine wire rods were produced by final heat treatment at 1180°C.
すなわち、一般に、Ｂ含有Ｎｌ基耐熱合金を加工するに
は、分塊鍛造温度、熱間加工温度、冷間引抜前の中間焼
鈍温度および最終熱処理温度は、１１５０〜１１８０℃
で実施されていたのである。That is, in general, to process a B-containing Nl-based heat-resistant alloy, the blooming forging temperature, hot working temperature, intermediate annealing temperature before cold drawing, and final heat treatment temperature are 1150 to 1180°C.
It was carried out in
ところが、上記溶解し鋳造して作製された例えばＢ ：
８０ｐｐｍ含有Ｎ１基耐熱合金インゴットを、温度：
１１８０℃で分塊鍛造して直径：１０ｍ＋＊のビレッ
トを作製し、上記ビレットを、温度： １１５０℃３０
分間保持後水冷の中間焼鈍−酸洗−冷間引抜を２回以上
繰返し、最終的に、温度： １１８０℃１時間保持後水
冷の中間焼鈍−酸洗−冷間引抜して直径＝１．６關の線
材を作製したところ、上記直径：１．１３ｍ＋ｓの線材
Ｂ含有量は、５ ｐｐｍに減少し、インゴットのＢ含有
量：８０ｐｐｍよりも大幅に少ないＢ含有量のＮｌ基耐
熱合金線材が作製されるという現象が生じたのである。However, for example, B manufactured by melting and casting as described above:
An N1 base heat-resistant alloy ingot containing 80 ppm was heated to a temperature of:
A billet with a diameter of 10m+* was produced by blooming at 1180°C, and the billet was heated at a temperature of 1150°C30.
After holding for 1 hour, water-cooling intermediate annealing, pickling, and cold drawing were repeated two or more times, and finally, after holding at 1180°C for 1 hour, water-cooling intermediate annealing, pickling, and cold drawing were performed to obtain a diameter of 1.6. When the wire of the connection was produced, the B content of the wire with the above diameter: 1.13 m+s was reduced to 5 ppm, and an Nl-based heat-resistant alloy wire with a B content significantly lower than the B content of the ingot: 80 ppm was produced. This phenomenon occurred.
すなわち、インゴットから線材に加工する途中で７５ｐ
ｐｓもの大幅なり含有量の減少が生じたのである。この
ような現象は、オーステナイト系Ｎ［基耐熱合金では、
従来、見出されていなかったのである。このような現象
は、特にＮｌ基耐熱合金の表面はど顕著に現れるので、
Ｂ含有Ｎｌ基耐熱合金インゴットから細線材、薄板、薄
肉管などを製造する場合に特に顕著に現れ、所定のＢ含
有量を有するＮ１基耐熱合金細線材、薄板、薄肉管など
が得られず、そのため高温クリープ特性など所望の機械
的特性が得られないという問題点が生じたのである。In other words, 75p is processed during processing from ingot to wire rod.
The content decreased significantly by as much as ps. This phenomenon occurs in austenitic N [based heat-resistant alloys,
This had not been discovered before. This phenomenon is particularly noticeable on the surface of Nl-based heat-resistant alloys, so
This is particularly noticeable when manufacturing thin wire rods, thin plates, thin-walled tubes, etc. from B-containing Nl-base heat-resistant alloy ingots, and N1-base heat-resistant alloy thin wire rods, thin plates, thin-walled tubes, etc. having a predetermined B content cannot be obtained. Therefore, a problem arose in that desired mechanical properties such as high-temperature creep properties could not be obtained.
そこで、本発明者らは、かかる問題点を解決すべく下記
のごとき研究を行った。Therefore, the present inventors conducted the following research in order to solve such problems.
まず、 Ｃ：０．０８％、 Ｃｒ：２１．９％。first, C: 0.08%, Cr: 21.9%.
Ｍｏ：９．０％、 Ｂ ：５０ｐｐＩ１
１゜を含有し、さらに、
Ｆ ｅ： １８．５％、 Ｗ ：０．４５
％。Mo: 9.0%, B: 50ppI1
1°, furthermore, Fe: 18.5%, W: 0.45
%.
Ｍ ｎ ： ０ 、９％、 Ｓ Ｉ：０．
３％。Mn: 0, 9%, SI: 0.
3%.
Ａ、ｌ！：０．０１％、 Ｔ！：０．０１
％。A, l! :0.01%, T! :0.01
%.
Ｃｏ：０．０１％、 Ｚ ｒ：０．００１
％。Co: 0.01%, Zr: 0.001
%.
Ｃａ：０．００２％。Ca: 0.002%.
を含有し、残り−Ｎ１および不可避不純物からなる組成
（以上、ｆｆｉ量％）を有し、厚さ： ２５ｍ＋＊から
なるＢ含有Ｎ１基耐熱合金板を用意した。A B-containing N1-based heat-resistant alloy plate having a composition (hereinafter, ffi amount %) containing -N1 and unavoidable impurities and having a thickness of 25 m+* was prepared.
このＢ含有Ｎ１基耐熱合金板を、温度： １０００℃。This B-containing N1-based heat-resistant alloy plate was heated to 1000°C.
１０５０℃、 １１００℃、 １１２５℃、 １
１５０℃、 １２００℃、 １２５０℃、の各温度
で、それぞれ大気中、２４時間保持の熱処理を行い、上
記Ｂ含有Ｎｌ基耐熱合金板表面より２ｍｍ内部における
Ｂ量を測定し、Ｂ量を縦軸に、温度を横軸にとり、グラ
フに表して、その結果を第１図に示した。1050℃, 1100℃, 1125℃, 1
Heat treatment was performed at each temperature of 150°C, 1200°C, and 1250°C for 24 hours in the air, and the amount of B was measured within 2 mm from the surface of the B-containing Nl-based heat-resistant alloy plate, and the amount of B was plotted on the vertical axis. The temperature was plotted on the horizontal axis and expressed in a graph, and the results are shown in FIG.
第１図の結果から、温度： １１２５℃より高い温度で
は、高温になるほどＢ量は、低減し、一方、温度： １
１２５℃以下ではＢ量はほとんど無視できる程度の減少
変化であることがわかる。これは、Ｂ量の変化は、炭化
物の熱的安定性と深く関わっており、炭化物が安定な熱
処理条件では、Ｂは主として炭化物中に一構成元素とし
て取込められるため、Ｂ量の変化は小さいが、炭化物が
固溶するような高温での熱処理条件では、Ｂは比較的速
い速度で外表面に拡散し、そこで外部の酸素と何らかの
酸化物を形成し、Ｎｌ基耐熱合金板の外にＢは逸散する
と推測され、後者の場合は、高温はどＢの逸散は速いも
のと考えられる。From the results in Figure 1, it can be seen that at temperatures higher than 1125°C, the amount of B decreases as the temperature increases;
It can be seen that below 125° C., the amount of B decreases to an almost negligible extent. This is because the change in the amount of B is deeply related to the thermal stability of the carbide, and under heat treatment conditions where the carbide is stable, B is mainly incorporated into the carbide as a constituent element, so the change in the amount of B is small. However, under high-temperature heat treatment conditions where carbides form a solid solution, B diffuses to the outer surface at a relatively high rate, where it forms some oxides with external oxygen, and B is released outside the Nl-based heat-resistant alloy plate. It is presumed that B will dissipate, and in the latter case, it is thought that B dissipates quickly due to the high temperature.
したがって、Ｂ含有Ｎｌ２Ｚ耐熱合金の分塊鍛造温度、
熱間加工温度、中間焼鈍および最終熱処理の保持温度を
、従来よりも低い温度： ｔｏｏ０〜１１２５℃に加熱
保持しながら加工することによりＢ含有量の減少は防止
できるという知見を得たのである。Therefore, the blooming temperature of the B-containing Nl2Z heat-resistant alloy,
It was discovered that the decrease in B content can be prevented by processing while maintaining the hot working temperature, intermediate annealing and final heat treatment temperatures at temperatures lower than conventional ones: too0 to 1125°C.
この発明は、かかる知見にもとづいてなされたものであ
って、
Ｃ：０．０４〜０．２５％
Ｃｒ：２０．０〜２５．０％
Ｍｏ：８．Ｏ〜１０．０％
Ｂ ：０．００１〜０．１％
を必須成分組成として含有するＢ含有Ｎ１基耐熱合金イ
ンゴットを、分塊鍛造してビレットまたはスラブなどの
加工素材を作製し、この加工素材を熱間鍛造、熱間圧延
などの熱間加工をしたのち、中間焼鈍、酸洗および冷間
加工を繰返すことにより小径線材、薄肉管または薄板を
加工し、必要に応じて最終熱処理する方法において、
上記分塊鍛造、熱間加工、中間焼鈍および最終熱処理を
、温度： １０００〜１１２５℃で行うＢ含有Ｎ１基耐
熱合金の塑性加工方法に特徴を有するものである。This invention was made based on this knowledge, and includes: C: 0.04-0.25% Cr: 20.0-25.0% Mo: 8. A B-containing N1-based heat-resistant alloy ingot containing O~10.0% B:0.001~0.1% as an essential component composition is forged into a processed material such as a billet or slab, and this processing is performed. A method of processing small-diameter wire rods, thin-walled tubes, or thin plates by subjecting the material to hot processing such as hot forging or hot rolling, and then repeating intermediate annealing, pickling, and cold processing, followed by final heat treatment if necessary. The present invention is characterized by a method for plastic working of a B-containing N1-based heat-resistant alloy, in which the above-mentioned bloom forging, hot working, intermediate annealing, and final heat treatment are performed at a temperature of 1000 to 1125°C.
上記Ｂ含有Ｎ１基耐熱合金においては、温度二１１２５
℃より高温度では、炭化物の安定性が悪く、合金素地中
に固溶したＢは、外表面に比較的大きな速度で拡散し逸
散する。そのため、加工に伴う熱処理温度は、１１２５
℃以下が好ましいが、一方、１０００℃より低温では、
続く塑性加工を行うための十分な軟化が得られず加工中
の割れ原因になる。In the above B-containing N1-base heat-resistant alloy, the temperature is 21125
At temperatures higher than 0.degree. C., the stability of the carbide is poor, and the B dissolved in the alloy matrix diffuses and evaporates to the outer surface at a relatively high rate. Therefore, the heat treatment temperature associated with processing is 1125
℃ or less is preferable, but on the other hand, at a temperature lower than 1000℃,
Sufficient softening for subsequent plastic working may not be obtained, leading to cracking during processing.
したがって、上記Ｂ含有Ｎ１基耐熱合金の熱処理温度お
よび塑性加工温度は、１０００〜１１２５℃が好ましい
。Therefore, the heat treatment temperature and plastic working temperature of the B-containing N1-based heat-resistant alloy are preferably 1000 to 1125°C.
この発明のＢ含有Ｎｉ基耐熱合金の必須成分を上記の如
く限定した理由は、次の通りである。The reason why the essential components of the B-containing Ni-based heat-resistant alloy of the present invention are limited as described above is as follows.
Ｃは、合金の素地を強化すると共に、ＭＯ。C strengthens the base of the alloy and also improves MO.
Ｃｒ、その他の炭化物形成元素と熱的安定性の高い炭化
物を形成し、さらにＢを炭化物中に取込み、熱処理によ
るＢ逸散防止上重要な元素であるが、その含有量が０，
０４重量％未満では所望の効果が得られず、一方、０．
２５重量％を越えて含有しても熱間加工性の劣化や高温
強度を損うので好ましくない。したがって、上記Ｂ含有
Ｎｉ基耐熱合金におけるＣ含有量は０．０４〜０．２５
重量％に定めた。It forms a highly thermally stable carbide with Cr and other carbide-forming elements, and is an important element for incorporating B into the carbide and preventing B dissipation during heat treatment.
If the amount is less than 0.04% by weight, the desired effect cannot be obtained;
If the content exceeds 25% by weight, it is not preferable because hot workability deteriorates and high-temperature strength is impaired. Therefore, the C content in the B-containing Ni-based heat-resistant alloy is 0.04 to 0.25.
It was determined as weight percent.
Ｃｒは、高温耐酸化性の向上や、炭化物の構成元素とし
て重要であるが、その含有量が２０．０重量％未満では
十分な効果が得られず、一方、２５．０重量％を越えて
添加すると、かえって機械的強度および加工性を劣化さ
せるので好ましくない。したがってＣ「含有量は、２０
．０〜２５．０重量％に定めた。Cr is important for improving high-temperature oxidation resistance and as a constituent element of carbides, but if its content is less than 20.0% by weight, sufficient effects cannot be obtained; on the other hand, if its content exceeds 25.0% by weight, Adding it is not preferable because it will actually deteriorate mechanical strength and workability. Therefore, the content of C is 20
．． The content was set at 0 to 25.0% by weight.
Ｍｏは、高温強度を高めるのに有用であり、また炭化物
の主たる構成元素としても重要であるが、その含有量が
８．０重量％未満では十分な効果が得られず、一方、１
０．０重量％を越えて含有すると熱間および冷間加工時
に割れが発生しやすいので好ましくない。したがって、
Ｍｏ含有量は８．０〜１０゜０重量％に定めた。Mo is useful for increasing high-temperature strength and is also important as a main constituent element of carbides, but if its content is less than 8.0% by weight, sufficient effects cannot be obtained;
If the content exceeds 0.0% by weight, cracks are likely to occur during hot and cold working, which is not preferable. therefore,
The Mo content was set at 8.0 to 10.0% by weight.
Ｂは、高温強度および延性を保持するために有用な元素
であるが、その含有量が０．００１重量％未満では所望
の効果が得られず、一方、０．１重量％を越えて添加す
ると熱間加工性や溶接性を損うので好ましくない。した
がって、Ｂ含有量は０．００１〜０．１重量％に定めた
。B is an element useful for maintaining high-temperature strength and ductility, but if the content is less than 0.001% by weight, the desired effect cannot be obtained, whereas if it is added in excess of 0.1% by weight, This is not preferable because it impairs hot workability and weldability. Therefore, the B content was set at 0.001 to 0.1% by weight.
なお、Ｎｂ、ＴａおよびＨ「は、Ｃｒ、Ｍｏと同じ様な
効果を有するので、Ｎｂ、ＴａおよびＨｆ’のうち１種
または２種以上を合計で５重量２６以下添加すると、Ｂ
の逸散防止にはさらに有効である。しかしながら上記Ｎ
ｂ、ＴａおよびＨｒのうち１種または２種以上の合計が
５重量％を越えて含まれると加工中に割れが発生するの
で好ましくない。Note that Nb, Ta, and H' have the same effect as Cr and Mo, so if one or more of Nb, Ta, and Hf' are added in a total of 5 weight 26 or less, B
It is even more effective in preventing the dissipation of However, the above N
If the total content of one or more of b, Ta, and Hr exceeds 5% by weight, cracks will occur during processing, which is undesirable.
つぎに、この発明を実施例にもとづいて具体的に説明す
る。Next, the present invention will be specifically explained based on examples.
実施例 １ ２０ｋｇ型の誘導真空溶解炉により溶解し、鋳造して、 Ｃ：０．１０％、 Ｃｒ：２２．０％。Example 1 Melted and cast in a 20kg type induction vacuum melting furnace, C: 0.10%, Cr: 22.0%.
Ｂ ：０．００８０％、 Ｍ ｏ ：
９ 、２％。B: 0.0080%, Mo:
9.2%.
Ｗ ：０．７％、 Ｍｎ＋０．７％。W: 0.7%, Mn+0.7%.
Ｓ Ｉ：０．４％、 Ｆｅ：１７．５％
。SI: 0.4%, Fe: 17.5%
.
ＡＩ：０．０２％、 ＴＩ：０．０４％
。AI: 0.02%, TI: 0.04%
.
Ｃｏ：０．０２％、 Ｚ ｒ：０
．００５ ％。Co: 0.02%, Zr: 0
．． 005%.
Ｃａ：０．００３ ％。Ca: 0.003%.
を含有し、残りＮ１および不可避不純物からなる組成（
以上、重量％）を有するＢ含有Ｎｉ基耐熱合金インゴッ
トを作製した。, and the remaining N1 and unavoidable impurities (
A B-containing Ni-based heat-resistant alloy ingot having a weight percentage of
このインゴットを、温度： １１２５℃にて分塊鍛造し
、直径： １０ｍｍのビレットを作製し、このビレット
を、温度二１１００℃３０分保持後熱間圧延して直径＝
８．２ｍｍの丸棒とし、この丸棒を、温度： １１００
℃３０分保持後３０分保持後鈍−酸洗−冷間引抜して直
径：８．２ｍｍの丸棒に縮径し、さらに上記直径：６．
２＋＋＋＋ｓの丸棒を温度： １１００℃２０分保持後
２０分保持後鈍−酸洗−冷間引抜の工程を２回繰返して
直径：３．２關の線材とし、最終的に、温度：１１２５
℃１時間保持後水冷の中間焼鈍−酸洗−冷間引抜して直
径：１．６ｍｍの細線材を作製した。This ingot was forged by blooming at a temperature of 1125°C to produce a billet with a diameter of 10 mm, and this billet was held at a temperature of 21100°C for 30 minutes and then hot rolled to have a diameter of 10 mm.
A round bar of 8.2 mm is heated to a temperature of 1100.
℃ for 30 minutes, and after holding for 30 minutes, it was blunt-pickled and cold-drawn to reduce the diameter to a round bar with a diameter of 8.2 mm, and further the above diameter: 6.
A round bar with a diameter of 2++++s was held at a temperature of 1100°C for 20 minutes, and then the process of dulling, pickling, and cold drawing was repeated twice to obtain a wire with a diameter of 3.2cm, and finally, a wire rod with a diameter of 3.2cm was obtained.
After holding at °C for 1 hour, water-cooled intermediate annealing, pickling, and cold drawing were performed to produce a thin wire material with a diameter of 1.6 mm.
このようにして得られた直径：１．６ｍｍのＢ含有ＮＩ
Ｍ耐熱合金細線材のＢ含有量を測定したところ、Ｂ ：
０．００７８重量９６であった。この結果から、イン
ゴットから細線材に加工する工程では脱Ｂ現象はほとん
どみられないことがわかる。Diameter thus obtained: 1.6 mm of B-containing NI
When the B content of M heat-resistant alloy thin wire rod was measured, B:
It was 0.0078 weight 96. From this result, it can be seen that almost no deboronization phenomenon is observed in the process of processing an ingot into a thin wire rod.
実施例 ２
実施例１で作製した直径：１０龍のビレットの中心軸に
直径：６ｍ＋ｓの穴を穿孔して素管を作製し、この素管
を温度： １０５０℃３０分保持後３０分保持後鈍を施
したのち酸洗し、冷間引抜機で引抜加工して厚さ：１．
Ｏｍｍの薄肉管を作製した。この薄肉管のＢ含有量を測
定したところ、Ｂ ： ０．００８０重量％であり、加
工中の脱Ｂ現象は全く認められなかった。Example 2 A hole with a diameter of 6 m + s was punched in the center axis of the billet with a diameter of 10 dragons prepared in Example 1 to prepare a blank tube, and this blank tube was held at a temperature of 1050°C for 30 minutes and then held for 30 minutes. After being dulled, it was pickled and then drawn using a cold drawing machine to a thickness of 1.
A thin-walled tube of 0 mm was fabricated. When the B content of this thin-walled tube was measured, it was found to be 0.0080% by weight, and no B removal phenomenon was observed during processing.
実施例 ３
実施例１で作製したインゴットを、温度： １１２５℃
で分塊鍛造し、厚さ＝１５關のスラブを作製した。Example 3 The ingot produced in Example 1 was heated to 1125°C.
A slab with a thickness of 15 mm was produced by blooming.
このスラブを温度： １１００℃で熱間圧延して厚さニ
アｍｍ板にし、上記厚さニア關の板を温度： １０５０
℃３０分保持後３０分保持後鈍を施したのち酸洗し、冷
間圧延して厚さ：４ｍｍの薄板を作製し、上記薄板を温
度： １０００℃２０分保持後２０分保持後鈍−酸洗−
冷間圧延の工程を３回繰返して最終的に厚さ二〇、５ｍ
＋＊の薄板を作製し、さらに温度： １１００℃２０分
保持の最終熱処理を施した。This slab was hot-rolled at a temperature of 1100°C to form a plate with a thickness of near mm, and a plate with a thickness near the above was rolled at a temperature of 1050°C.
After being held at 1000°C for 20 minutes, dulled after being held for 30 minutes, and then pickled and cold rolled to produce a thin plate with a thickness of 4 mm. Pickling-
The cold rolling process was repeated three times to obtain a final thickness of 20.5 m.
A thin plate of +* was produced and further subjected to final heat treatment at 1100°C for 20 minutes.
このようにして得られた厚さ：０．５ｍｍの薄板のＢ含
有量を測定したところ、Ｂ ： ０．００７９重量％で
、上記インゴットのＢ含有量とほとんど変らず、加工中
におけるＢの逸散はほとんど見られないことがわかる。When the B content of the thus obtained thin plate with a thickness of 0.5 mm was measured, it was found to be 0.0079% by weight, which was almost the same as the B content of the above ingot, indicating that B was lost during processing. It can be seen that scattering is hardly seen.
この発明によると、重量％で、
Ｃ：０．０４〜０．２５％、 Ｃｒ：２０．０〜
２５．０％。According to this invention, in weight %, C: 0.04 to 0.25%, Cr: 20.0 to
25.0%.
Ｍｏ：８．Ｏ〜１０．０％、 Ｂ ：０．００
１〜ｏ、ｉ％。Mo:8. O~10.0%, B: 0.00
1-o, i%.
を必須成分として含有するＢ含有Ｎ１基耐熱合金をＢが
逸散することなく大気中で塑性加工することができるの
で、安定して目標のＢ含有量を有するＢ含有Ｎｌ基耐熱
合金製細線材、薄板、薄肉管などの素材を製造すること
ができ、Ｂ、１有量の不足に伴う不良素材の発生が皆無
になるなどのすぐれた効果を奏するものである。The B-containing N1-based heat-resistant alloy, which contains B-containing N1-base heat-resistant alloy as an essential component, can be plastic-worked in the atmosphere without B escaping, so that the B-containing N1-base heat-resistant alloy thin wire material stably has the target B content. , thin plates, thin-walled tubes, etc., and has excellent effects such as eliminating the occurrence of defective materials due to lack of B and 1.
第１図は、大気中熱処理温度と表面Ｂ含有量の関係を示
すグラフである。FIG. 1 is a graph showing the relationship between atmospheric heat treatment temperature and surface B content.
Claims (1)
ンゴットを、分塊鍛造してビレットまたはスラブなどの
加工素材を作製し、この加工素材を熱間鍛造、熱間圧延
などの熱間加工をしたのち、中間焼鈍、酸洗および冷間
加工を繰返すことにより小径線材、薄肉管または薄板を
加工し、必要に応じて最終熱処理する方法において、 上記分塊鍛造、熱間加工、中間焼鈍および最終熱処理を
、温度：１０００〜１１２５℃で行うことを特徴とする
Ｂ含有Ｎｉ基耐熱合金の塑性加工方法。(1) Obtained by melting and casting, weight % C: 0.04-0.25% Cr: 20.0-25.0% Mo: 8.0-10.0% B: 0.001 A B-containing Ni-based heat-resistant alloy ingot containing ~0.1% as an essential component is forged into a processed material such as a billet or slab, and this processed material is subjected to hot forging, hot rolling, etc. After hot working, a small diameter wire rod, thin-walled tube or thin plate is processed by repeating intermediate annealing, pickling and cold working, and if necessary, a final heat treatment is performed. A method for plastic working of a B-containing Ni-based heat-resistant alloy, characterized in that intermediate annealing and final heat treatment are performed at a temperature of 1000 to 1125°C.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1068868A JP2722628B2 (en) | 1989-03-20 | 1989-03-20 | Plastic working method for B-containing Ni-base heat-resistant alloy |
| US07/495,290 US5019179A (en) | 1989-03-20 | 1990-03-19 | Method for plastic-working ingots of heat-resistant alloy containing boron |
| EP90105246A EP0388892B1 (en) | 1989-03-20 | 1990-03-20 | Method for plastic-working ingots of heat-resistant alloy containing boron |
| DE69013192T DE69013192T2 (en) | 1989-03-20 | 1990-03-20 | Process for the plastic deformation of blocks made of heat-resistant boron-containing alloy. |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1068868A JP2722628B2 (en) | 1989-03-20 | 1989-03-20 | Plastic working method for B-containing Ni-base heat-resistant alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02247365A true JPH02247365A (en) | 1990-10-03 |
| JP2722628B2 JP2722628B2 (en) | 1998-03-04 |
Family
ID=13386064
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1068868A Expired - Lifetime JP2722628B2 (en) | 1989-03-20 | 1989-03-20 | Plastic working method for B-containing Ni-base heat-resistant alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2722628B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007084895A (en) * | 2005-09-26 | 2007-04-05 | Nippon Yakin Kogyo Co Ltd | Ni-base alloy material with excellent workability and high temperature strength, and its manufacturing method |
| WO2019004176A1 (en) * | 2017-06-30 | 2019-01-03 | 日立金属株式会社 | Method for manufacturing ni-based heat-resistant superalloy wire, and ni-based heat-resistant superalloy wire |
| CN115125339A (en) * | 2022-07-15 | 2022-09-30 | 丹阳市海威电热合金有限公司 | Ultra-high temperature nickel-based alloy and preparation method thereof |
| CN117535559A (en) * | 2024-01-10 | 2024-02-09 | 北京北冶功能材料有限公司 | Low-density nickel-based high-temperature alloy foil and preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS559940A (en) * | 1978-07-05 | 1980-01-24 | Matsushita Electric Ind Co Ltd | Washable furniture |
| JPS6240336A (en) * | 1985-08-13 | 1987-02-21 | Mitsubishi Metal Corp | Ni-fe-cr alloy sheet material superior in cold formability and its manufacture |
| JPS63149361A (en) * | 1986-12-11 | 1988-06-22 | Nippon Yakin Kogyo Co Ltd | Manufacture of iron-nickel alloy |
-
1989
- 1989-03-20 JP JP1068868A patent/JP2722628B2/en not_active Expired - Lifetime
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS559940A (en) * | 1978-07-05 | 1980-01-24 | Matsushita Electric Ind Co Ltd | Washable furniture |
| JPS6240336A (en) * | 1985-08-13 | 1987-02-21 | Mitsubishi Metal Corp | Ni-fe-cr alloy sheet material superior in cold formability and its manufacture |
| JPS63149361A (en) * | 1986-12-11 | 1988-06-22 | Nippon Yakin Kogyo Co Ltd | Manufacture of iron-nickel alloy |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007084895A (en) * | 2005-09-26 | 2007-04-05 | Nippon Yakin Kogyo Co Ltd | Ni-base alloy material with excellent workability and high temperature strength, and its manufacturing method |
| WO2019004176A1 (en) * | 2017-06-30 | 2019-01-03 | 日立金属株式会社 | Method for manufacturing ni-based heat-resistant superalloy wire, and ni-based heat-resistant superalloy wire |
| US11085104B2 (en) | 2017-06-30 | 2021-08-10 | Hitachi Metals, Ltd. | Method for manufacturing Ni-based heat-resistant superalloy wire, and Ni-based heat-resistant super alloy wire |
| CN115125339A (en) * | 2022-07-15 | 2022-09-30 | 丹阳市海威电热合金有限公司 | Ultra-high temperature nickel-based alloy and preparation method thereof |
| CN117535559A (en) * | 2024-01-10 | 2024-02-09 | 北京北冶功能材料有限公司 | Low-density nickel-based high-temperature alloy foil and preparation method and application thereof |
| CN117535559B (en) * | 2024-01-10 | 2024-05-07 | 北京北冶功能材料有限公司 | Low-density nickel-based high-temperature alloy foil and preparation method and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2722628B2 (en) | 1998-03-04 |
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