JPH03240930A - Heat-resistant alloy excellent in carburizing resistance and weldability - Google Patents
Heat-resistant alloy excellent in carburizing resistance and weldabilityInfo
- Publication number
- JPH03240930A JPH03240930A JP3676290A JP3676290A JPH03240930A JP H03240930 A JPH03240930 A JP H03240930A JP 3676290 A JP3676290 A JP 3676290A JP 3676290 A JP3676290 A JP 3676290A JP H03240930 A JPH03240930 A JP H03240930A
- Authority
- JP
- Japan
- Prior art keywords
- weldability
- resistant alloy
- heat
- alloy
- resistance
- 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
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 18
- 239000000956 alloy Substances 0.000 title claims abstract description 18
- 238000005255 carburizing Methods 0.000 title abstract description 9
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 abstract description 32
- 229910052799 carbon Inorganic materials 0.000 abstract description 5
- 238000004519 manufacturing process Methods 0.000 abstract description 5
- 229910052758 niobium Inorganic materials 0.000 abstract description 5
- VGGSQFUCUMXWEO-UHFFFAOYSA-N Ethene Chemical compound C=C VGGSQFUCUMXWEO-UHFFFAOYSA-N 0.000 abstract description 4
- 239000005977 Ethylene Substances 0.000 abstract description 4
- 238000005336 cracking Methods 0.000 abstract description 3
- 230000000694 effects Effects 0.000 description 22
- 238000003466 welding Methods 0.000 description 16
- 230000007423 decrease Effects 0.000 description 14
- 150000001247 metal acetylides Chemical class 0.000 description 8
- 230000007774 longterm Effects 0.000 description 7
- 230000003647 oxidation Effects 0.000 description 5
- 238000007254 oxidation reaction Methods 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- 238000006243 chemical reaction Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000003878 thermal aging Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 229910001149 41xx steel Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は石油化学工業におけるエチレン製造用クランキ
ングチューブ材料等として有用な耐浸炭性および溶接性
にすぐれた耐熱合金に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a heat-resistant alloy with excellent carburization resistance and weldability that is useful as a cranking tube material for ethylene production in the petrochemical industry.
エチレン製造用反応管は、多数の直管をベンド管を介し
て接続すると共に、要所にＴ字型管、Ｙ字型管等の異形
管を組込むことにより構成される。A reaction tube for ethylene production is constructed by connecting a large number of straight tubes through bend tubes and incorporating irregularly shaped tubes such as T-shaped tubes and Y-shaped tubes at important points.
上記配管構成に使用される管材は、その高温高圧操業に
耐え得る機械的性質や耐酸化性等を必要とすることは言
うまでもなく、更には、管内反応系から析出する固形炭
素が管壁面に付着することに伴う浸炭に対する抵抗性を
備えていなければならない。浸炭が生じると、その進行
に伴う管材質の経時変化、特に延性の著しい低下を生じ
、高圧操業条件下、脆化による管体の割れ発生の危険が
増大するからである。It goes without saying that the pipe materials used in the above piping configuration must have mechanical properties and oxidation resistance that can withstand high-temperature, high-pressure operation, and furthermore, solid carbon precipitated from the reaction system inside the pipe adheres to the pipe wall surface. It must be resistant to carburization associated with carburization. This is because when carburization occurs, as carburization progresses, the quality of the pipe material changes with time, particularly a significant decrease in ductility, and the risk of cracking of the pipe body due to embrittlement increases under high pressure operating conditions.
また、上記管材は、長時間（例えば１〜５年）の使用過
程でクリープや曲がり等の変形が不可避的に生起するの
で、その変形により、例えば炉床にガイドがつかえる等
の支障を生じるような場合には、その修復作業として、
変形部分の切断除去と、その部分を再接合するための溶
接が施される。In addition, the above-mentioned pipe material inevitably undergoes deformation such as creep and bending during long-term use (for example, 1 to 5 years), so such deformation may cause problems such as the guide getting stuck in the hearth. In such cases, as part of the repair work,
The deformed parts are cut and removed and welded to rejoin them.
従って、その管材は、長時間の熱時効をうけた後にも良
好な溶接性を有する材質でなければならない。Therefore, the tube material must be made of a material that has good weldability even after being subjected to long-term thermal aging.
従来より上記管材料として、ＡＳＴＭ ＨＰ材（０，
４Ｃ−２５Ｃｒ −３５Ｎ ｉ −Ｆ ｅ ）およびそ
の改良材（０，４Ｃ−２５Ｃｒ−３５Ｎｉ−Ｎｂ、 Ｗ
、 Ｍ。Conventionally, ASTM HP material (0,
4C-25Cr-35Ni-Fe) and its improved material (0,4C-25Cr-35Ni-Nb, W
, M.
Ｆｅ）等の耐熱合金が貫用されてきた。Heat-resistant alloys such as Fe) have been widely used.
ＨＰ材は、９００〜１０５０°Ｃの温度範囲で使用され
る材料であり、それを越える温度域での耐浸炭性は十分
といえない。HP material is a material used in a temperature range of 900 to 1050°C, and cannot be said to have sufficient carburization resistance in a temperature range exceeding this.
他方、ＨＰ改良材は、１１００″Ｃまでの温度域におい
てすぐれた材料特性を示し、耐浸炭性も良好であるが、
長時間使用後の溶接性が悪く、溶接部に割れを生じ易い
という問題がある。これは、長期使用過程での延性の低
下が大きく、伸びは使用前の約１０〜１５％から、わず
か２〜３％程度にまで減少するため、溶接時の溶接収縮
応力が拘束されることに生として起因していることが判
明した。なお、同材料は改良された浸炭抵抗性を有して
いるとは言え、長期使用過程で微量浸炭（約０．１〜０
゜３％Ｃの増量）を生じ、これによる延性低下も、上記
溶接性の劣化を大きくしている。On the other hand, the HP improved material shows excellent material properties in the temperature range up to 1100''C and has good carburization resistance, but
There is a problem that weldability is poor after long-term use, and cracks are likely to occur in the welded part. This is because the ductility decreases significantly during long-term use, and the elongation decreases from about 10 to 15% before use to only about 2 to 3%, which limits the welding shrinkage stress during welding. It was found that this was caused by a raw material. Although the same material has improved carburization resistance, a small amount of carburization (approximately 0.1 to 0.0
The resulting decrease in ductility also increases the aforementioned deterioration in weldability.
本発明は、上記問題を解決するためになされたものであ
り、前記ＨＰ改良材を凌ぐ浸炭抵抗性を有すると共に、
１０００°Ｃをこえる高温域での長時間使用後にも良好
な溶接性を有する改良された耐熱合金を提供する。The present invention was made to solve the above problems, and has carburization resistance superior to the above-mentioned HP improving material, and
To provide an improved heat-resistant alloy that has good weldability even after long-term use in a high temperature range exceeding 1000°C.
〔課題を解決するための手段および作用〕本発明の耐熱
合金は、Ｃ：０．０８％以上、０．３％未満、 Ｓ ｉ
：０．５〜３％、Ｍｎ：５％以下、Ｃｒ：２３〜３９
％、Ｎｉ：３５〜６０％、Ｎ：０．２５％以下、および
Ｎｂ：０．２〜２％、 Ｍｏ ：０．５〜４％、Ｗ：０
．５〜１０％から選ばれる１種ないし２種以上、残部実
質的にＦｅからなり、所望により、Ｆｅの一部が、Ａ
ｌ ： ０．０２〜０．６％、 Ｔ ｉ ：０．０１〜
０．５％。[Means and effects for solving the problems] The heat-resistant alloy of the present invention contains C: 0.08% or more and less than 0.3%, Si
: 0.5-3%, Mn: 5% or less, Cr: 23-39
%, Ni: 35-60%, N: 0.25% or less, and Nb: 0.2-2%, Mo: 0.5-4%, W: 0
．． One or more selected from 5 to 10%, the remainder substantially consisting of Fe, and if desired, a part of Fe may be A.
l: 0.02~0.6%, Ti: 0.01~
0.5%.
Ｚｒ：０．０１〜０．５％から選ばれる１種ないし２種
以上の元素で置換された化学組成を有している。Zr: has a chemical composition substituted with one or more elements selected from 0.01 to 0.5%.
本発明の耐熱合金の成分限定理由は次のとおりである。The reasons for limiting the ingredients of the heat-resistant alloy of the present invention are as follows.
Ｃ： ０．０８％以上、０．３％未満
Ｃは、鋳造凝固時に、Ｃｒ、Ｍｏ、Ｗ等の炭化物を粒界
に形成し、またオーステナイト相に固溶したＣは部材の
実使用時の加熱を受けてＣｒ炭化物を形成する。これら
の炭化物の分散効果によりクリープ破断強度が高められ
る。しかし、その量が０．０８％に満たないと、１０５
０〜１１００°Ｃの高温使用における十分なりリープ破
断強度およびクリープ強度を確保することができない。C: 0.08% or more, less than 0.3% C forms carbides such as Cr, Mo, W, etc. at grain boundaries during casting and solidification, and C dissolved in the austenite phase forms carbides during casting and solidification. Upon heating, Cr carbide is formed. Creep rupture strength is increased by the dispersion effect of these carbides. However, if the amount is less than 0.08%, 105
It is not possible to ensure sufficient leap rupture strength and creep strength when used at high temperatures of 0 to 1100°C.
添加量の増加に伴って効果を増すが、反面多量添加に伴
い、Ｃｒ炭化物の多量の析出により、室温伸び特性が低
下し、使用後の部材同士の溶接性が低下するので、０．
３％未満とする。The effect increases as the amount added increases, but on the other hand, when a large amount is added, a large amount of Cr carbide precipitates, resulting in a decrease in room temperature elongation properties and a decrease in weldability between members after use.
Less than 3%.
Ｓｉ：０．５〜３％
Ｓｉは脱酸作用、および溶湯の流動性向上・鋳造性改善
効果を有するほか、高温使用時の加熱により部材表面に
Ｓｉｎ、の被膜を形成し、Ｃの侵入を抑制する。その効
果は、０．５％から認められる。しかし、３％を越えて
多量に添加すると、クリープ破断強度の低下および溶接
性の低下きたすので、３％を上限とする。Si: 0.5-3% Si not only has a deoxidizing effect and the effect of improving the fluidity of molten metal and improving castability, but also forms a film of Si on the surface of parts when heated during high-temperature use, preventing the intrusion of C. suppress. The effect is recognized from 0.5%. However, if added in a large amount exceeding 3%, the creep rupture strength and weldability will decrease, so the upper limit is set at 3%.
Ｍｎ ： ５％以下
Ｍｎは脱酸作用を有すると共に、ＳをＭｎＳとして固定
することにより、溶接性の向上に奏効する。これらの効
果は５％までの添加により得られ、それを越えて添加す
る必要はない。Mn: 5% or less Mn has a deoxidizing effect and is effective in improving weldability by fixing S as MnS. These effects can be obtained by adding up to 5%, and there is no need to add more than that.
Ｃｒ：２３〜３９％
Ｃｒは耐酸化性および高温強度を高め、また耐浸炭性の
向上に奏効する。１０５０℃をこえる高温域、特に１１
００°Ｃ付近での使用における耐浸炭性および耐酸化性
等を確保するためには、少なくとも２３％の添加を必要
とする。添加増量に伴ってその効果を増すが、あまり多
くすると、高温使用過程でのＣｒ炭化物の析出量の増加
により、使用後の引張延性の著しい低下を招くので、３
９％を上限とする。Cr: 23-39% Cr increases oxidation resistance and high temperature strength, and is effective in improving carburization resistance. High temperature range exceeding 1050℃, especially 11
In order to ensure carburization resistance, oxidation resistance, etc. when used at temperatures around 00°C, it is necessary to add at least 23%. The effect increases as the amount is increased, but if it is added too much, the amount of Cr carbide precipitated during high-temperature use will increase, resulting in a significant decrease in tensile ductility after use.
The upper limit is 9%.
Ｎｉ：３５〜６０％
Ｎｉは、Ｃｒ、Ｆｅ等と共にオーステナイト地を形成し
、組織の安定化、耐酸化性の向上に寄与するほか、長時
間の高温使用過程におけるＣｒ炭化物の安定性を高める
（１次炭化物の球状化および２次炭化物の成長抑制）効
果を有する。また、部材表面の酸化被膜を安定化するこ
とにより耐浸炭性を高める。特に、クランキングチュー
ブとして１１５０”Ｃまでの高温使用における耐浸炭性
を確保するには、少な（とも３５％の添加を必要とする
。Ni: 35-60% Ni forms an austenitic matrix together with Cr, Fe, etc., and contributes to stabilizing the structure and improving oxidation resistance, as well as increasing the stability of Cr carbide during long-term high-temperature use ( It has the effect of spheroidizing primary carbides and inhibiting the growth of secondary carbides. Furthermore, carburization resistance is improved by stabilizing the oxide film on the surface of the member. In particular, in order to ensure carburization resistance when used as a cranking tube at high temperatures up to 1150''C, a small amount (at least 35%) is required.
添加増量に伴って効果を増すが、６０％をこえると、耐
浸炭性の改善効果はほぼ飽和する。このため６０％を上
限とする。The effect increases as the amount added increases, but when it exceeds 60%, the effect of improving carburization resistance is almost saturated. Therefore, the upper limit is set at 60%.
Ｎ ： ０．２５％以下
Ｎはオーステナイト地中に固溶して高温引張強度を高め
る。しかし、多量添加は室温引張延性の低下をきたすの
で、０．２５％を上限とする。N: 0.25% or less N forms a solid solution in the austenite and increases high-temperature tensile strength. However, since adding a large amount causes a decrease in room temperature tensile ductility, the upper limit is set at 0.25%.
Ｎｂ：０．２〜２％
Ｎｂは、鋳造凝固時に、（Ｎｂ、Ｔｉ）炭化物を粒界に
形成する。その炭化物の存在によりクリープにおける粒
界破壊抵抗性が高められ、クリープ破断寿命が増大する
。その効果は０．２％以上の添加により現れる。しかし
多量添加に伴って却ってクリープ破断強度が低下し、ま
た耐酸化性も悪くなるので、２％を上限とする。Nb: 0.2-2% Nb forms (Nb, Ti) carbides at grain boundaries during casting and solidification. The presence of the carbide increases intergranular fracture resistance in creep and increases creep rupture life. The effect appears when 0.2% or more is added. However, as the addition of a large amount increases, the creep rupture strength decreases and the oxidation resistance deteriorates, so the upper limit is set at 2%.
Ｍｏ：０．５〜４％
ＭＯはオーステナイト地の固溶強化と、Ｃｒ−Ｍｏ系炭
化物の形成による粒界強化とにより高温引張強度を高め
る。この効果は０．５％以上の添加により得られる。し
かし、あまり多くなると、ＣｒＭｏ系炭化物の析出量が
過剰となり、引張延性の低下をきたすので、４％を上限
とする。Mo: 0.5 to 4% MO increases high-temperature tensile strength by solid solution strengthening of the austenite base and grain boundary strengthening through the formation of Cr-Mo carbides. This effect can be obtained by adding 0.5% or more. However, if the amount is too large, the amount of precipitated CrMo-based carbides becomes excessive, resulting in a decrease in tensile ductility, so the upper limit is set at 4%.
Ｗ：０．５〜ｌＯ％
Ｗは、前記ＭＯと同じようにオーステナイト地の固溶強
化と、粒界の炭化物析出による粒界強化によって高温引
張強度を高める。そＱ効果は添加量的０．５％から現れ
る。添加増量に伴って耐浸炭性も向上するが、１０％を
こえると、室温引張延性の著しい低下をきたすので、１
０％を上限とする。W: 0.5 to 1O% W increases high-temperature tensile strength by solid solution strengthening of austenitic base and grain boundary strengthening due to carbide precipitation at grain boundaries, similar to the above-mentioned MO. The Q effect appears from an addition amount of 0.5%. Carburization resistance also improves as the amount is increased, but if it exceeds 10%, the room temperature tensile ductility decreases significantly.
The upper limit is 0%.
本発明合金は、上記諸元素のほかに、所望により、Ｔｉ
、Ｚｒ、およびＡＩから選ばれる１種ないし２種以上の
元素を含有する。In addition to the above-mentioned elements, the alloy of the present invention optionally contains Ti.
, Zr, and AI.
Ａ １ ： ０．０２〜０．６％
ＡＩは、高温域において部材表面にＡＩ酸化物被膜を形
成し、浸炭雰囲気からのＣの侵入を抑制する効果を有す
る。この耐浸炭性改善効果を得るには少なくとも０．０
２％の添加を必要とする。添加増量によりその効果を増
すが、あまり多くなると、鋳造性が損なわれ、また引張
延性が低下するので、０．６％を上限とする。A1: 0.02 to 0.6% AI forms an AI oxide film on the surface of the member in a high temperature range, and has the effect of suppressing the intrusion of C from the carburizing atmosphere. To obtain this carburization resistance improvement effect, at least 0.0
Requires addition of 2%. The effect can be increased by increasing the amount added, but if the amount is too large, castability will be impaired and tensile ductility will be lowered, so the upper limit is set at 0.6%.
Ｔ ｉ ： ０．０１〜０．５％
Ｔｉは、部材の実使用時の加熱下におけるＣｒ炭化物の
成長粗大化を抑制遅延させることによりクリープ破断強
度の向上に寄与する。この効果は０．０１％以上の添加
により得られる。しかし、多量添加に伴って酸化物系介
在物の増量および析出物の粗大化等により却ってクリー
プ破断強度の低下をきたするで、０．５％を上限とする
。Ti: 0.01 to 0.5% Ti contributes to improving the creep rupture strength by suppressing and delaying the coarsening of Cr carbide during heating during actual use of the member. This effect can be obtained by adding 0.01% or more. However, if a large amount is added, the creep rupture strength will decrease due to an increase in the amount of oxide inclusions and coarsening of precipitates, so the upper limit is set at 0.5%.
Ｚ ｒ ： ０．０１〜０．５％
Ｚｒはオーステナイト地の固溶強化により、クリープ破
断強度を高める。この効果は０．０１％以上の添加によ
り現れ、添加増量に伴ってその効果を増す。しかし、０
．５％をこえると、合金の清浄度が悪くなり却ってクリ
ープ破断強度の低下をきたす。このため、０．５％を上
限とする。Zr: 0.01 to 0.5% Zr increases the creep rupture strength by solid solution strengthening of the austenitic base. This effect appears when 0.01% or more is added, and the effect increases as the amount added increases. However, 0
．． If it exceeds 5%, the cleanliness of the alloy deteriorates and the creep rupture strength actually decreases. Therefore, the upper limit is set at 0.5%.
なお、通常の溶製技術上不可避的に混入する不純物はこ
の種の鋼に許容される範囲内で混在して差し支えなく、
例えば０．０３％以下のＰ、０．０３％以下のＳの混在
によって本発明の趣旨が損なわれることはない。In addition, impurities that are unavoidable due to normal melting technology may be mixed within the allowable range for this type of steel.
For example, the gist of the present invention is not impaired by the presence of 0.03% or less of P and 0.03% or less of S.
高周波誘導溶解炉で溶製した合金溶湯を、遠心力鋳造に
付して供試管材を得た。管サイズ（機械加工後）は、外
径１２２ｍｍ、肉厚１０ｍｍ、長さ５２０ｍ＋ｓである
。各供試管材の化学成分組成を第１表に示す。A molten alloy produced in a high-frequency induction melting furnace was subjected to centrifugal force casting to obtain a test tube material. The pipe size (after machining) is an outer diameter of 122 mm, a wall thickness of 10 mm, and a length of 520 m+s. The chemical composition of each test tube material is shown in Table 1.
表中、Ｎ１１ｌ〜９は発明例、Ｎａ １０１．１０２は
比較例である。比較例阻１０１．１１ｋＬ１０２は、い
ずれも代表的従来材である改良ＨＰ相当材である。In the table, N111-9 are invention examples, and Na 101.102 is a comparative example. Comparative Example 101.11kL102 are all materials equivalent to improved HP, which are typical conventional materials.
各供試管材について、浸炭試験および熱時効後の溶接試
験を行った。A carburizing test and a welding test after thermal aging were conducted for each test tube material.
（Ｉ）浸炭試験
試験片（１２φＸ６０Ｉ！、 ａｍ）を固体浸炭剤（デ
グサＫＧ３０）中に埋覆して加熱し、８５０″Ｃから１
１５０°Ｃまで３０Ｈｒを要して昇温させ、１１５０°
Ｃに１８Ｈｒ保持したのち室温まで降温させるヒートパ
タンを１７回反復実施（試験時間： （３０Ｈｒ＋１
８Ｈｒ） Ｘ １０７＝ ８１６Ｈｒ ）。試験後、試
験片表面から５鵬の深さまで、０．５ ｗａのピッチで
切粉を採取し、化学分析により各深さ位置における炭素
増加量を求める。(I) Carburizing test A test piece (12φX60I!, am) was buried in a solid carburizing agent (Degussa KG30) and heated, and heated from 850″C to 1°C.
It took 30 hours to raise the temperature to 150°C, and then it was heated to 1150°.
A heat pattern in which the temperature was maintained at C for 18 hours and then cooled to room temperature was repeated 17 times (test time: (30 hours + 1
8Hr) x 107=816Hr). After the test, chips were collected at a pitch of 0.5 wa from the surface of the test piece to a depth of 5 mm, and the amount of carbon increase at each depth position was determined by chemical analysis.
〔■〕熟熱時効後溶接試験
供試管材を、１１００″Ｃｘ１年間の熱時効処理に付し
たのち、時効処理管材同士の突合せ端部を０字開先とし
ＧＴＡＷ溶接による突合せ溶接を行った。[■] Welding test after aging The test tubes were subjected to thermal aging treatment at 1100″C for 1 year, and then butt welding was performed by GTAW welding with the butt ends of the aged tubes made into a zero-shaped bevel.
（１）開先形状
開先角度：２０°、ルート半径＝５閣、ルート面：１．
６■、ルートギャップ：０Ｗ
（２）溶接姿勢 水平
（３）溶接棒
発明例の管材の溶接には溶接棒（ａ）、比較例の管材の
溶接には溶接棒（ｂ）を使用（溶接棒径はいずれも２．
４＋＋ｗ）
！：Ｃ０，４９％、Ｓｉ１．５５％、 Ｍ ｎ １．
３４％。(1) Bevel shape Bevel angle: 20°, root radius = 5 degrees, root surface: 1.
6■, Root gap: 0W (2) Welding posture Horizontal (3) Welding rod Welding rod (a) is used to weld the pipe material of the invention example, welding rod (b) is used to weld the pipe material of the comparative example (welding rod Both diameters are 2.
4++w)! :C0.49%, Si1.55%, Mn1.
34%.
Ｐ Ｏ，００８％、 Ｓ Ｏ，００３％、Ｃｒ２５．
３％、Ｎｉ３５．１％、Ｎｂ１．２２％、 Ｗｌ、２８
％、Ｍｏ０．３２％、残部Ｆｅ。PO,008%, SO,003%, Cr25.
3%, Ni35.1%, Nb1.22%, Wl, 28
%, Mo0.32%, balance Fe.
ＭＪｊｉＪ！Ｄ；Ｌ：Ｃ０，４９％、Ｓｉ１．７８％、
Ｍ ｎ １．０４％。MJjiJ! D; L: C0.49%, Si1.78%,
Mn 1.04%.
Ｐ Ｏ，００５％、 Ｓ Ｏ，００３％、Ｃｒ３０．
２％、Ｎｉ４２．６％、Ｎｂ１．３６％、残部Ｆｅ。PO,005%, SO,003%, Cr30.
2%, Ni 42.6%, Nb 1.36%, balance Fe.
（４）溶接電流：８０〜１３０Ａ、溶接速度７５〜１２
０ｍ／分。(4) Welding current: 80-130A, welding speed 75-12
0m/min.
（５）肉盛層数：５層
１記浸炭試験結果を第１図〔Ｉ〕 （供試合金阻１〜５
）および同図〔■］ （供試合金Ｎ１１６〜９およびＮ
ｏ、１０１．１０２）に、溶接試験結果を第２表にそれ
ぞれ示す、第２表中、「○」は割れ発生のないことを表
している。(5) Number of overlay layers: 5 layers 1 The results of the carburizing test are shown in Figure 1 [I]
) and the same figure [■] (sample gold N116-9 and N
101, 102) and welding test results are shown in Table 2. In Table 2, "○" indicates that no cracking occurred.
上記試験結果から明らかなように、本発明の耐熱合金は
、代表的な従来材であるＨＰ改良材（阻１０１、階１０
２）に比べて、１１００℃をこえる高温域における耐浸
炭性にすぐれており、また高温長時間の熱時効後におけ
る溶接性も良好で、従来のＨＰ改良材（Ｎ１１１０１．
Ｎα１０２）では初層溶接の熱影響部（ＨＡＺ）に割れ
を生じているのに対し、発明例の管材はいずれも割れの
発生は皆無で、健全な溶接継手が形成されている。As is clear from the above test results, the heat-resistant alloy of the present invention is a typical conventional material with improved HP
Compared to the conventional HP improved material (N11101.
In Nα102), cracks occurred in the heat-affected zone (HAZ) of the first layer weld, whereas in the pipe materials of the invention examples, no cracks occurred at all, and sound welded joints were formed.
溶接試験結果
〔発明の効果〕
本発明の耐熱合金は、１０００°Ｃを越える高温域にお
いて従来材であるＨＰ材やその改良材を凌ぐ材料特性を
有しており、１１５０℃付近においても卓抜した耐浸炭
性を示し、また高温長時間の熱時効をうけた後にも良好
な溶接性を保有している。従って、エチレン製造用反応
管材料等として有用であり、高温高圧および浸炭環境に
おける反応管の耐久性・安全性が高められ、また長時間
使用により変形等を生じた場合にも、その修復のための
溶接において健全な溶接継手を形成することができ、修
復後の安全な使用を可能にするものである。なお、本発
明の耐熱合金は、リフオーマチューブあるいはラジアン
トチューブ、ハースローラ等の各種高温用構造材料とし
ても有用である。Welding test results [Effects of the invention] The heat-resistant alloy of the present invention has material properties that surpass those of the conventional material HP material and its improved materials in the high temperature range exceeding 1000°C, and has outstanding properties even at temperatures around 1150°C. It exhibits carburization resistance and maintains good weldability even after being subjected to long-term thermal aging at high temperatures. Therefore, it is useful as a material for reaction tubes for ethylene production, etc., increasing the durability and safety of reaction tubes in high-temperature, high-pressure, and carburizing environments. It is possible to form a sound welded joint during welding, and to enable safe use after repair. The heat-resistant alloy of the present invention is also useful as a structural material for various high-temperature applications such as refoma tubes, radiant tubes, and hearth rollers.
【図面の簡単な説明】
第１図（Ｉ）（ＩＩ）は浸炭試験片の深さ方向の炭素濃
度分布を示すグラフである。[Brief Description of the Drawings] Figures 1 (I) and (II) are graphs showing the carbon concentration distribution in the depth direction of a carburized test piece.
Claims (1)
〜３％、Ｍｎ：５％以下、Ｃｒ：２３〜３９％、Ｎｉ：
３５〜６０％、Ｎ：０．２５％以下、およびＮｂ：０．
２〜２％、Ｍｏ：０．５〜４％、Ｗ：０．５〜１０％か
ら選ばれる１種ないし２種以上、残部実質的にＦｅから
なる耐浸炭性および溶接性にすぐれた耐熱合金、２、Ｃ
：０．０８％以上、０．３％未満、Ｓｉ：０．５〜３％
、Ｍｎ：５％以下、Ｃｒ：２３〜３９％、Ｎｉ：３５〜
６０％、Ｎ：０．２５％以下、並びにＮｂ：０．２〜２
％、Ｍｏ：０．５〜４％、Ｗ：０．５〜１０％から選ば
れる１種ないし２種以上、およびＡｌ：０．０２〜０．
６％、Ｔｉ：０．０１〜０．５％、Ｚｒ：０．０１〜０
．５％から選ばれる１種ないし２種以上、残部実質的に
Ｆｅからなる耐浸炭性および溶接性にすぐれた耐熱合金
。1, C: 0.08% or more, less than 0.3%, Si: 0.5
~3%, Mn: 5% or less, Cr: 23-39%, Ni:
35-60%, N: 0.25% or less, and Nb: 0.
A heat-resistant alloy with excellent carburization resistance and weldability, consisting of one or more selected from 2% to 2%, Mo: 0.5% to 4%, W: 0.5% to 10%, and the remainder substantially Fe. ,2,C
: 0.08% or more, less than 0.3%, Si: 0.5-3%
, Mn: 5% or less, Cr: 23-39%, Ni: 35-35%
60%, N: 0.25% or less, and Nb: 0.2-2
%, Mo: 0.5-4%, W: 0.5-10%, and Al: 0.02-0.
6%, Ti: 0.01-0.5%, Zr: 0.01-0
．． A heat-resistant alloy with excellent carburization resistance and weldability, consisting of one or more selected from 5% and the remainder substantially Fe.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3676290A JPH03240930A (en) | 1990-02-16 | 1990-02-16 | Heat-resistant alloy excellent in carburizing resistance and weldability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3676290A JPH03240930A (en) | 1990-02-16 | 1990-02-16 | Heat-resistant alloy excellent in carburizing resistance and weldability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03240930A true JPH03240930A (en) | 1991-10-28 |
Family
ID=12478764
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3676290A Pending JPH03240930A (en) | 1990-02-16 | 1990-02-16 | Heat-resistant alloy excellent in carburizing resistance and weldability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03240930A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0765948A2 (en) * | 1995-09-29 | 1997-04-02 | Kubota Corporation | Heat-resistant Ni-Cr alloy |
| JP2003073745A (en) * | 2001-08-31 | 2003-03-12 | Kawasaki Steel Corp | Hearth roll for annealing furnace for stainless steel sheet |
| GB2542519B (en) * | 2014-07-10 | 2020-04-08 | Paralloy Ltd | Low ductility alloy |
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|---|---|---|---|---|
| JPS4927725A (en) * | 1972-07-08 | 1974-03-12 | ||
| JPS5395822A (en) * | 1977-01-31 | 1978-08-22 | Roach Donald Brian | Highhstrength* heattresistant alloy for casting use |
| JPS54125118A (en) * | 1978-03-22 | 1979-09-28 | Pompey Acieries | Nickel * chromium alloy having very high carburizing resistance under extreme high temperature condition |
| JPS57116759A (en) * | 1981-06-13 | 1982-07-20 | Kubota Ltd | Heat resistant cast steel |
| JPS57116758A (en) * | 1981-06-13 | 1982-07-20 | Kubota Ltd | Heat resistant cast steel |
| JPS57116761A (en) * | 1981-06-13 | 1982-07-20 | Kubota Ltd | Heat resistant cast steel |
| JPS57116760A (en) * | 1981-06-13 | 1982-07-20 | Kubota Ltd | Heat resistant cast steel |
| JPS5873751A (en) * | 1981-10-27 | 1983-05-04 | Mitsubishi Heavy Ind Ltd | Carburization resistant and heat resistant cast steel |
| JPS58197248A (en) * | 1975-12-02 | 1983-11-16 | アチエリエ・デユ・マノワル・ポンペイ | Heat resistant alloy |
| JPS61186446A (en) * | 1985-02-14 | 1986-08-20 | Kubota Ltd | Heat resistant alloy |
| JPH03236448A (en) * | 1989-12-28 | 1991-10-22 | Toshiba Corp | Cr-ni series heat resistant steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4927725A (en) * | 1972-07-08 | 1974-03-12 | ||
| JPS58197248A (en) * | 1975-12-02 | 1983-11-16 | アチエリエ・デユ・マノワル・ポンペイ | Heat resistant alloy |
| JPS5395822A (en) * | 1977-01-31 | 1978-08-22 | Roach Donald Brian | Highhstrength* heattresistant alloy for casting use |
| JPS54125118A (en) * | 1978-03-22 | 1979-09-28 | Pompey Acieries | Nickel * chromium alloy having very high carburizing resistance under extreme high temperature condition |
| JPS57116759A (en) * | 1981-06-13 | 1982-07-20 | Kubota Ltd | Heat resistant cast steel |
| JPS57116758A (en) * | 1981-06-13 | 1982-07-20 | Kubota Ltd | Heat resistant cast steel |
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| JPS61186446A (en) * | 1985-02-14 | 1986-08-20 | Kubota Ltd | Heat resistant alloy |
| JPH03236448A (en) * | 1989-12-28 | 1991-10-22 | Toshiba Corp | Cr-ni series heat resistant steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0765948A2 (en) * | 1995-09-29 | 1997-04-02 | Kubota Corporation | Heat-resistant Ni-Cr alloy |
| EP0765948A3 (en) * | 1995-09-29 | 1997-11-05 | Kubota Corporation | Heat-resistant Ni-Cr alloy |
| JP2003073745A (en) * | 2001-08-31 | 2003-03-12 | Kawasaki Steel Corp | Hearth roll for annealing furnace for stainless steel sheet |
| GB2542519B (en) * | 2014-07-10 | 2020-04-08 | Paralloy Ltd | Low ductility alloy |
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