JP2001247940A - Heat resistant alloy excellent in carburizing resistance and metal dusting resistance - Google Patents
Heat resistant alloy excellent in carburizing resistance and metal dusting resistanceInfo
- Publication number
- JP2001247940A JP2001247940A JP2000061535A JP2000061535A JP2001247940A JP 2001247940 A JP2001247940 A JP 2001247940A JP 2000061535 A JP2000061535 A JP 2000061535A JP 2000061535 A JP2000061535 A JP 2000061535A JP 2001247940 A JP2001247940 A JP 2001247940A
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- Prior art keywords
- resistance
- tube
- carburizing
- metal dusting
- resistant alloy
- Prior art date
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、直接還元製鉄炉の
リヒータチューブ、エチレン製造用クラッキングチュー
ブ等の管材として好適な耐熱合金に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a heat-resistant alloy suitable as a tube material such as a reheater tube for a direct reduction steelmaking furnace and a cracking tube for ethylene production.
【０００２】[0002]
【従来の技術】直接還元製鉄プロセスでは、水素を用い
て鉄鉱石(酸化鉄)を還元することにより金属鉄が製造さ
れる。還元後の排ガスは、水素、一酸化炭素、水蒸気等
を含んでおり、約４５０〜７５０℃の温度に加熱された
リヒータチューブの中を通り再使用に供される。エチレ
ン製造プロセスでは、約１０００〜１２００℃の温度に
加熱されたクラッキングチューブの中を、液状又はガス
状の炭化水素を通過させて熱分解が行われる。このリヒ
ータチューブ、クラッキングチューブとして、Ｃｒ及び
Ｎｉを多量に含有するＦｅ−Ｃｒ−Ｎｉ系耐熱合金が広
く使用されている。2. Description of the Related Art In a direct reduction iron making process, metallic iron is produced by reducing iron ore (iron oxide) using hydrogen. The exhaust gas after reduction contains hydrogen, carbon monoxide, water vapor and the like, and is reused through a reheater tube heated to a temperature of about 450 to 750 ° C. In the ethylene production process, pyrolysis is performed by passing a liquid or gaseous hydrocarbon through a cracking tube heated to a temperature of about 1000 to 1200 ° C. As the reheater tube and the cracking tube, Fe—Cr—Ni heat-resistant alloys containing a large amount of Cr and Ni are widely used.
【０００３】[0003]
【発明が解決しようとする課題】直接還元製鉄用リヒー
タチューブの場合、継続的に使用していると、チューブ
の一部が減肉する問題がある。この減肉は、メタルダス
ティングと称される現象で、チューブ内面での浸炭脆化
に原因があると考えられており、約４５０〜７５０℃の
温度域で生じ易い。すなわち、水素と一酸化炭素を含む
還元性ガスが加熱されると、ＣＯ＋Ｈ2→Ｃ＋Ｈ2Ｏ、２
ＣＯ→ＣＯ2＋Ｃの反応が起こり、カーボンが析出して
チューブ内面に付着する。カーボンは、チューブ内へ侵
入して浸炭が起こる。浸炭部では、Ｃｒ炭化物が形成さ
れるため、マトリックス中のＣｒ量が減少する結果、水
素を含む環境下で材質が脆化し、金属がダストのように
崩落する。チューブの減肉が著しくなると、チューブの
交換を余儀なくされる。また、エチレン製造用クラッキ
ングチューブの場合も、原料炭化水素からカーボンが不
可避的に析出し、チューブ内面に付着するため、高温で
の浸炭が進行すると管材質の劣化が起こる。それゆえ、
この種用途の材料にあっては、耐浸炭性及び耐メタルダ
スティング性の向上が要請されている。In the case of a reheater tube for direct reduction steelmaking, there is a problem that if the tube is continuously used, a part of the tube is reduced in thickness. This thinning is a phenomenon called metal dusting, which is considered to be caused by carburizing embrittlement on the inner surface of the tube, and easily occurs in a temperature range of about 450 to 750 ° C. That is, when the reducing gas containing hydrogen and carbon monoxide is heated, CO + H 2 → C + H 2 O, 2
A reaction of CO → CO 2 + C occurs, and carbon is deposited and adheres to the inner surface of the tube. The carbon penetrates into the tube and causes carburization. In the carburized part, a Cr carbide is formed, so that the amount of Cr in the matrix is reduced. As a result, the material is embrittled in an environment containing hydrogen, and the metal collapses like dust. If the thickness of the tube is significantly reduced, the tube must be replaced. Also, in the case of cracking tubes for ethylene production, carbon inevitably precipitates from the raw material hydrocarbons and adheres to the inner surface of the tubes. Therefore, if carburization at a high temperature proceeds, deterioration of the tube material occurs. therefore,
Materials of this type are required to have improved resistance to carburization and metal dusting.
【０００４】[0004]
【課題を解決するための手段】本発明は、重量％にて、
Ｃ：０.０５〜０.６％、Ｓｉ：２.５％以下、Ｍｎ：１.
５〜６％、Ｃｒ：２３〜４６％、Ｎｉ：２３〜５０％、
並びに、Ｗ：６％以下、Ｎｂ：２％以下及びＭｏ：２％
以下からなる群から選択される少なくとも１種を含み、
残部実質的にＦｅからなり、耐浸炭性及び耐メタルダス
ティング性にすぐれる耐熱合金を提供する。本発明の耐
熱合金は、必要に応じて、Ｃｅ：０.００５〜０.２５
％、Ａｌ：０.０１〜０.５％、Ｔｉ：０.０１〜０.４
％、Ｚｒ：０.０１〜０.３％を必要に応じて含むことが
できる。SUMMARY OF THE INVENTION The present invention provides, in weight percent,
C: 0.05-0.6%, Si: 2.5% or less, Mn: 1.0%
5-6%, Cr: 23-46%, Ni: 23-50%,
And W: 6% or less, Nb: 2% or less, and Mo: 2%
Including at least one selected from the group consisting of:
The present invention provides a heat-resistant alloy consisting essentially of Fe and having excellent carburization resistance and metal dusting resistance. The heat-resistant alloy of the present invention may contain Ce: 0.005 to 0.25, if necessary.
%, Al: 0.01 to 0.5%, Ti: 0.01 to 0.4
%, Zr: 0.01 to 0.3% as necessary.
【０００５】[0005]
【成分限定理由の説明】Ｃ：０.０５〜０.６％ Ｃは鋳造凝固時に結晶粒界にＮｂＣ又はＣｒ−Ｗ系炭化
物を形成し、粒界を強化してクリープ破断強度を高め
る。クリープ破断強度の向上は０.０５％から認められ
るが、０.６％を越えると常温引張延性が低下するた
め、含有量は０.０５〜０.６％とする。[Explanation of Reasons for Restricting Components] C: 0.05-0.6% C forms NbC or Cr-W-based carbide at the crystal grain boundaries at the time of casting and solidification, strengthens the grain boundaries and increases the creep rupture strength. The improvement in creep rupture strength is recognized from 0.05%, but if it exceeds 0.6%, the room-temperature tensile ductility decreases, so the content is made 0.05 to 0.6%.
【０００６】Ｓｉ：２.５％以下 Ｓｉは脱酸作用を有し、溶湯の流動性を高めると共に、
耐浸炭性を向上させる効果がある。約１２００℃までの
浸炭腐食環境において、表面近傍に内部酸化膜ＳｉＯ2
を形成して、Ｃ侵入のバリアとしての効果を有する。含
有量の増加と共に効果を増すが、２.５％を越えるとク
リープ破断強度が著しく低下する。よって上限を２.５
％に規定する。なお、１.３〜２.０％が好ましい。[0006] Si: 2.5% or less Si has a deoxidizing effect, increases the fluidity of the molten metal,
It has the effect of improving carburization resistance. In a carburizing corrosion environment up to about 1200 ° C, an internal oxide film SiO 2
And has an effect as a barrier for C intrusion. The effect increases as the content increases, but if it exceeds 2.5%, the creep rupture strength is significantly reduced. Therefore, the upper limit is 2.5
%. In addition, 1.3-2.0% is preferable.
【０００７】Ｍｎ：１.５〜６％ Ｍｎは、Ｓを固定する作用があり、溶接性を向上させ
る。また、マトリックスに固溶し、密着性の強いＭｎ酸
化物を金属表面に形成して耐浸炭性及び耐メタルダステ
ィング性を向上させる効果がある。このため、１.５％
以上含有させる。一方、６％を越えるとクリープ破断強
度が低下するため、上限は６％に規定する。なお、３.
５〜５％が好ましく、４〜５％がより好ましい。Mn: 1.5 to 6% Mn has an effect of fixing S and improves weldability. In addition, there is an effect that a Mn oxide which forms a solid solution in the matrix and has high adhesion is formed on the metal surface to improve carburization resistance and metal dusting resistance. Therefore, 1.5%
It is contained above. On the other hand, if it exceeds 6%, the creep rupture strength decreases, so the upper limit is set to 6%. Note that 3.
5-5% is preferable, and 4-5% is more preferable.
【０００８】Ｃｒ：２３〜４６％ Ｃｒは耐酸化性の向上に寄与する。約１２００℃までの
使用温度において、Ｎｉとの共存下で耐酸化性を確保す
るために２３％以上必要とする。しかし、Ｎｉとのバラ
ンスにおいて、４６％を越えると常温引張延伸びの低下
が著しくなるため、４６％を上限とする。[0008] Cr: 23 to 46% Cr contributes to the improvement of oxidation resistance. At an operating temperature up to about 1200 ° C., 23% or more is required to ensure oxidation resistance in the presence of Ni. However, if it exceeds 46% in the balance with Ni, the drop in the room temperature tensile stretching becomes remarkable, so the upper limit is 46%.
【０００９】Ｎｉ：２３〜５０％ Ｎｉはオーステナイト相を安定化し、耐酸化性と高温強
度の確保に有効である。約１２００℃までの高温使用を
考慮すると２３％以上必要である。しかし、５０％を越
えて含有しても対応する高温強度の向上は望めないの
で、５０％を上限とする。Ni: 23 to 50% Ni stabilizes the austenite phase and is effective for securing oxidation resistance and high-temperature strength. Considering the use of high temperatures up to about 1200 ° C., 23% or more is required. However, if the content exceeds 50%, a corresponding improvement in high-temperature strength cannot be expected, so the upper limit is 50%.
【００１０】Ｗ、Ｎｂ、Ｍｏは、少なくとも１種以上を
含有させる。 Ｗ：６％以下 Ｗはマトリックスに固溶すると共に、Ｃｒ−Ｗ系炭化物
を形成してクリープ破断強度の向上に寄与する。含有量
の増加と共にその効果を増すが、６％を越えると常温引
張伸びの低下が著しくなるので、上限は６％とする。[0010] At least one of W, Nb and Mo is contained. W: 6% or less W forms a solid solution with the matrix and forms a Cr-W-based carbide to contribute to improvement in creep rupture strength. The effect increases as the content increases, but if it exceeds 6%, the tensile elongation at room temperature is significantly reduced, so the upper limit is 6%.
【００１１】Ｎｂ：２％以下 Ｎｂはクリープ破断強度の向上に寄与する。しかし、２
％を越えると常温引張伸びの低下を招くので、上限は２
％とする。Nb: 2% or less Nb contributes to improvement in creep rupture strength. However, 2
%, The tensile elongation at room temperature is lowered.
%.
【００１２】Ｍｏ：２％以下 Ｍｏはクリープ破断強度の向上に寄与し、高温引張強度
を向上させる。しかし、２％を越えると常温引張伸びの
低下を招くので、上限は２％とする。Mo: 2% or less Mo contributes to improvement in creep rupture strength and improves high temperature tensile strength. However, if it exceeds 2%, the tensile elongation at room temperature is reduced, so the upper limit is set to 2%.
【００１３】Ｃｅ：０.００５〜０.２５％ ＣｅはＣＯ−Ｈ2−Ｈ2Ｏの還元性雰囲気において、耐浸
炭性及び耐メタルダスティング性を向上させる。このた
め、必要に応じて０.００５％以上含有させることが好
ましい。しかし、含有量が０.２５％を越えると、鋳造
時に酸化物を生成して鋼の清浄度の低下が大きくなるた
め、上限は０.２５％とする。Ce: 0.005 to 0.25% Ce improves carburization resistance and metal dusting resistance in a reducing atmosphere of CO—H 2 —H 2 O. For this reason, it is preferable to contain 0.005% or more as needed. However, if the content exceeds 0.25%, oxides are formed during casting and the cleanliness of the steel is greatly reduced, so the upper limit is 0.25%.
【００１４】Ａｌ：０.０１〜０.５％ Ａｌは耐浸炭性を向上させる効果があるので、必要に応
じて０.０１％以上含有させる。しかし、含有量が０.５
％を越えると強度低下を招く。このため、含有量は０.
０１〜０.５％が好ましい。Al: 0.01 to 0.5% Al has an effect of improving the carburization resistance, so that 0.01% or more is contained as necessary. However, the content is 0.5
%, The strength is reduced. Therefore, the content is 0.1.
It is preferably from 0.01 to 0.5%.
【００１５】Ｔｉ：０.０１〜０.４％ Ｔｉはクリープ破断強度の向上に寄与するため、必要に
応じて０.０１％以上含有させる。しかし、含有量が０.
４％を越えると、常温引張延性の低下を招くので上限は
０.４％とする。Ti: 0.01 to 0.4% Ti contributes to the improvement of creep rupture strength, so it is contained in 0.01% or more as necessary. However, when the content is 0.1.
If it exceeds 4%, the room-temperature tensile ductility is reduced, so the upper limit is made 0.4%.
【００１６】Ｚｒ：０.０１〜０.３％ Ｚｒはクリープ破断強度の向上に寄与するため、必要に
応じて０.０１％以上含有させる。しかし、含有量が０.
３％を越えると、常温引張延性の低下を招くので上限は
０.３％とする。Zr: 0.01-0.3% Since Zr contributes to the improvement of creep rupture strength, it is contained at 0.01% or more as necessary. However, when the content is 0.1.
If it exceeds 3%, the room-temperature tensile ductility decreases, so the upper limit is made 0.3%.
【００１７】本発明の耐熱合金は、上記成分元素を含有
し、残部は実質的にＦｅからなる。なお、合金の溶製時
に不可避的に混入する不純物であっても、この種の合金
に通常許容される範囲内であれば、存在しても構わな
い。例えば、Ｐ、Ｓについては、Ｐ：０.２％以下、
Ｓ：０.２％以下の含有は許容される。The heat-resistant alloy of the present invention contains the above-mentioned component elements, and the balance substantially consists of Fe. It should be noted that impurities that are inevitably mixed during the melting of the alloy may be present as long as they are within the range normally allowed for this kind of alloy. For example, for P and S, P: 0.2% or less,
S: Content of 0.2% or less is allowable.
【００１８】[0018]
【実施例】直接還元製鉄のリヒータチューブがメタルダ
スティングを受ける温度範囲は約４５０〜７５０℃の比
較的低い温度域であるため、６００℃で浸炭試験を実施
し、耐浸炭性及び耐メタルダスティング性を調べた。エ
チレン製造用クラッキングチューブの加熱温度は約１０
００〜１１５０℃の高い温度域であるため、１０００℃
で浸炭試験を実施し、耐浸炭性を調べた。さらに、高温
引張クリープ破断試験を行ない、クリープ破断強度を調
べた。[Example] Since the temperature range in which the reheater tube of the direct reduction steel is subjected to metal dusting is a relatively low temperature range of about 450 to 750 ° C, a carburizing test was conducted at 600 ° C, and the carburizing resistance and the metal resistance were evaluated. The dusting property was examined. The heating temperature of the cracking tube for ethylene production is about 10
Because of the high temperature range of 00 to 1150 ° C, 1000 ° C
A carburizing test was conducted to examine the carburizing resistance. Further, a high temperature tensile creep rupture test was performed to examine the creep rupture strength.
【００１９】６００℃での浸炭試験 表１に示す合金化学成分の供試材を溶製し、得られた供
試材から幅２０mm×長さ３０mm×厚さ５mmの試験片を切
り出した。試験片は、長さ方向の端縁から７.５mm、幅
方向の端縁から１０mmの位置に直径５mmの貫通孔を形成
した後、＃４００のエメリーペーパを用いて表面を滑ら
かに仕上げた。なお、表１中、No.１〜No.１２は発明例
であり、No.１３〜No.１６はＭｎ量が少ない比較例であ
る。直接還元製鉄のリヒータチューブ内を流通するＣＯ
リッチのＣＯ−Ｈ2−Ｈ2Ｏガスをシミュレートしたガス
として、ＣＯ：０.０６リットル／分、Ｈ2：０.０２リ
ットル／分の混合ガスを２５℃の加湿器に通した後、実
験炉内へ供給した。各試験片は、重量測定を行なった
後、孔の中に直径４mmの棒を通して、６００℃の温度の
実験炉の中で吊り下げた。９００時間経過後、試験片を
実験炉から取り出し、表面の付着物を毛ブラシできれい
にこすり取り、超音波洗浄を行なった後、再び重量測定
を行なった。測定結果を試験片１cm2当たりの重量変化
に換算し、その重量変化量を表２に記載している。 Carburizing test at 600 ° C. Test materials having the alloy chemical components shown in Table 1 were melted, and test pieces having a width of 20 mm × length 30 mm × thickness 5 mm were cut out from the obtained test materials. The test piece was formed with a through-hole having a diameter of 5 mm at a position 7.5 mm from the edge in the length direction and 10 mm from the edge in the width direction, and the surface was finished smoothly using # 400 emery paper. In Table 1, No. 1 to No. 12 are invention examples, and No. 13 to No. 16 are comparative examples having a small amount of Mn. CO flowing through the reheater tube of direct reduction steelmaking
As a gas simulating a rich CO—H 2 —H 2 O gas, a mixed gas of CO: 0.06 L / min and H 2 : 0.02 L / min was passed through a humidifier at 25 ° C. It was supplied into the experimental furnace. Each specimen was weighed and then suspended in a laboratory furnace at a temperature of 600 ° C. by passing a rod having a diameter of 4 mm into the hole. After a lapse of 900 hours, the test piece was taken out of the experimental furnace, and the adhered substance on the surface was rubbed cleanly with a bristle brush, subjected to ultrasonic cleaning, and weighed again. The measurement result was converted into a weight change per 1 cm 2 of the test piece, and the weight change amount is shown in Table 2.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】表２を参照すると、比較例のNo.１５とNo.
１６は、発明例のNo.１〜No.１２と比べて、重量増加が
多く、浸炭が進行していることを示している。比較例の
No.１３とNo.１４は重量が減少している。これは、メタ
ルダスティング現象による金属の崩落を生じたためであ
る。すなわち、Ｍｎの含有量が少ないため浸炭が進んで
Ｃｒ炭化物の生成量が多くなり、またＣｒの含有量が２
４〜２５％と少な目であることから、マトリックス中の
Ｃｒ濃度が低下して、材質の脆化を起こしたためと考え
られる。なお、前述のNo.１５とNo.１６は、No.１３とN
o.１４よりもＣｒの含有量が多いため、浸炭が起こって
も、マトリックス中のＣｒ濃度の低下が材質の脆化を起
こすまでに至っていない。このように、Ｍｎ酸化物は金
属表面での密着性が強く、耐浸炭性、さらには耐メタル
ダスティング性に非常に有効であることがわかる。発明
例の中でもNo.１とNo.２の重量増加が若干多くなってい
るのは、Ｃｒの含有量が少な目であることによる。それ
ゆえ、耐浸炭性を向上させるには、Ｃｒの含有量は約３
０％を越えることが望ましく、約３５％以上がさらに望
ましい。Referring to Table 2, the comparative examples No. 15 and No. 15
No. 16 shows that the weight increase is large and carburization is progressing as compared with No. 1 to No. 12 of the invention examples. Comparative example
No. 13 and No. 14 have reduced weight. This is because metal collapse occurred due to the metal dusting phenomenon. That is, since the content of Mn is small, carburization proceeds and the amount of generated Cr carbide increases, and the content of Cr becomes 2%.
This is considered to be because the concentration of Cr in the matrix was reduced due to the small amount of 4 to 25%, and the material was embrittled. Note that No. 15 and No. 16 described above are No. 13 and N
Since the content of Cr is higher than that of o.14, even if carburization occurs, the decrease in the Cr concentration in the matrix has not yet led to embrittlement of the material. Thus, it can be seen that the Mn oxide has strong adhesion on the metal surface, and is very effective in carburization resistance and metal dusting resistance. Among the invention examples, the reason why the weight increase of No. 1 and No. 2 is slightly increased is that the content of Cr is small. Therefore, in order to improve carburization resistance, the content of Cr should be about 3%.
Desirably, it exceeds 0%, and more preferably, about 35% or more.
【００２３】１０００℃浸炭試験 エチレン製造用分解炉のクラッキングチューブを流通す
るＣＨ4−Ｈ2−Ｈ2Ｏガスをシミュレートしたガスとし
て、ＣＨ4：０.０６リットル／分、Ｈ2：０.０３リット
ル／分の混合ガスを３４℃の加湿器に通した後、実験炉
内へ供給した。各試験片は、メタルダスティング試験と
同じように重量測定を行なった後、孔の中に直径４mmの
棒を通して、１０００℃の温度の実験炉の中で吊り下げ
た。１２５時間経過後、試験片を実験炉から取り出し、
表面の付着物を毛ブラシできれいにこすり取り、超音波
洗浄を行なった後、再び重量測定を行なった。重量変化
量を表２に併せて記載している。 1000 ° C. carburizing test As a gas simulating CH 4 —H 2 —H 2 O gas flowing through a cracking tube of a cracking furnace for ethylene production, CH 4 : 0.06 liter / min, H 2 : 0. After passing a mixed gas of 03 L / min through a humidifier at 34 ° C., it was supplied into the experimental furnace. Each specimen was weighed in the same manner as in the metal dusting test, and then suspended in a laboratory furnace at a temperature of 1000 ° C. through a rod having a diameter of 4 mm in the hole. After a lapse of 125 hours, remove the test specimen from the experimental furnace,
The attached matter on the surface was rubbed cleanly with a bristle brush, and after ultrasonic cleaning, the weight was measured again. The amount of change in weight is also shown in Table 2.
【００２４】表２を参照すると、No.１３〜No.１６の重
量増加は、No.１〜No.１２よりも多く、耐浸炭性に劣る
ことを示している。これはＭｎの含有量が少ないためで
ある。Referring to Table 2, the weight increase of No. 13 to No. 16 was larger than that of No. 1 to No. 12, indicating that the carburization resistance was inferior. This is because the content of Mn is small.
【００２５】高温クリープ破断試験 表１に示す合金化学成分の供試材から、直径６mm、標点
間長さ３０mmの試験片を切り出し、試験温度９８２℃、
応力３４.３Nの条件にて引張クリープ破断試験(ＪＩＳ
Ｚ ２２７２)を行ない、破断時間を測定した。測定結果
を表２に併せて記載している。発明例は、直接還元製鉄
炉のリヒータチューブ、エチレン製造用分解炉のクラッ
キングチューブとして必要な高温強度を具えている。 High temperature creep rupture test A test piece having a diameter of 6 mm and a length between gauge points of 30 mm was cut out from a test material having the chemical composition of the alloy shown in Table 1.
Tensile creep rupture test under the condition of stress 34.3N (JIS
Z 2272), and the rupture time was measured. The measurement results are also shown in Table 2. The invention example has the high temperature strength required for a reheater tube of a direct reduction steelmaking furnace and a cracking tube of a cracking furnace for ethylene production.
【００２６】[0026]
【発明の効果】本発明の耐熱合金は、耐浸炭性及び耐メ
タルダスティング性にすぐれているから、直接還元製鉄
炉のリヒータチューブとして好適である。また、高温で
の浸炭性にすぐれているから、エチレン製造用分解炉の
クラッキングチューブとしても適している。The heat-resistant alloy of the present invention is excellent in carburization resistance and metal dusting resistance, and thus is suitable as a reheater tube of a direct reduction iron making furnace. Further, since it has excellent carburizing properties at high temperatures, it is also suitable as a cracking tube for a cracking furnace for ethylene production.
Claims (3)
ｉ：２.５％以下、Ｍｎ：１.５〜６％、Ｃｒ：２３〜４
６％、Ｎｉ：２３〜５０％、並びに、Ｗ：６％以下、Ｎ
ｂ：２％以下及びＭｏ：２％以下からなる群から選択さ
れる少なくとも１種を含み、残部実質的にＦｅである耐
浸炭性及び耐メタルダスティング性にすぐれる耐熱合
金。(1) C: 0.05 to 0.6% by weight, S
i: 2.5% or less, Mn: 1.5 to 6%, Cr: 23 to 4
6%, Ni: 23 to 50%, and W: 6% or less, N
b: A heat-resistant alloy containing at least one selected from the group consisting of 2% or less and Mo: 2% or less, and the balance being substantially Fe, which is excellent in carburization resistance and metal dusting resistance.
Ａｌ：０.０１〜０.５％を含んでいる請求項１に記載の
耐熱合金。2. The heat-resistant alloy according to claim 1, which contains 0.005 to 0.25% of Ce and / or 0.01 to 0.5% of Al.
ｒ：０.０１〜０.３％を含んでいる請求項１又は請求項
２に記載の耐熱合金。3. Ti: 0.01 to 0.4% and / or Z
The heat-resistant alloy according to claim 1 or 2, wherein r: 0.01 to 0.3% is contained.
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|---|---|---|---|
| JP2000061535A JP3895089B2 (en) | 2000-03-07 | 2000-03-07 | Heat resistant alloy with excellent carburization and metal dusting resistance |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000061535A JP3895089B2 (en) | 2000-03-07 | 2000-03-07 | Heat resistant alloy with excellent carburization and metal dusting resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2001247940A true JP2001247940A (en) | 2001-09-14 |
| JP3895089B2 JP3895089B2 (en) | 2007-03-22 |
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|---|---|---|---|
| JP2000061535A Expired - Lifetime JP3895089B2 (en) | 2000-03-07 | 2000-03-07 | Heat resistant alloy with excellent carburization and metal dusting resistance |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2002103072A1 (en) * | 2001-06-19 | 2002-12-27 | Sumitomo Metal Industries, Ltd. | Metal material having good resistance to metal dusting |
| JP2006075841A (en) * | 2004-09-07 | 2006-03-23 | Sumitomo Metal Ind Ltd | Welded joint and welding material |
| WO2007052782A1 (en) * | 2005-10-31 | 2007-05-10 | Kubota Corporation | HEAT-RESISTANT ALLOY CAPABLE OF DEPOSITING FINE Ti-Nb-Cr CARBIDE OR Ti-Nb-Zr-Cr CARBIDE |
| JP2010236010A (en) * | 2009-03-31 | 2010-10-21 | Kubota Corp | Nb-CONTAINING AUSTENITIC HEAT RESISTANT STEEL EXCELLENT IN CREEP RESISTANCE AFTER AGING |
| CN105200338A (en) * | 2014-05-30 | 2015-12-30 | 中国石油化工股份有限公司 | Anti-coking alloy material and use thereof |
| CN107326217A (en) * | 2017-06-27 | 2017-11-07 | 西北工业大学 | A kind of ni-fe-based alloy of high-carbon containing niobium and preparation method |
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2000
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2002103072A1 (en) * | 2001-06-19 | 2002-12-27 | Sumitomo Metal Industries, Ltd. | Metal material having good resistance to metal dusting |
| US6623869B1 (en) | 2001-06-19 | 2003-09-23 | Sumitomo Metal Ind | Metal material having good resistance to metal dusting |
| JP2006075841A (en) * | 2004-09-07 | 2006-03-23 | Sumitomo Metal Ind Ltd | Welded joint and welding material |
| JP4513466B2 (en) * | 2004-09-07 | 2010-07-28 | 住友金属工業株式会社 | Welded joints and welding materials |
| WO2007052782A1 (en) * | 2005-10-31 | 2007-05-10 | Kubota Corporation | HEAT-RESISTANT ALLOY CAPABLE OF DEPOSITING FINE Ti-Nb-Cr CARBIDE OR Ti-Nb-Zr-Cr CARBIDE |
| US7959854B2 (en) | 2005-10-31 | 2011-06-14 | Kubota Corporation | Heat resistant alloy adapted to precipitate fine Ti-Nb-Cr carbide or Ti-Nb-Zr-Cr carbide |
| JP5213450B2 (en) * | 2005-10-31 | 2013-06-19 | 株式会社クボタ | Heat-resistant alloy for depositing fine Ti-Nb-Cr carbide or Ti-Nb-Zr-Cr carbide |
| JP2010236010A (en) * | 2009-03-31 | 2010-10-21 | Kubota Corp | Nb-CONTAINING AUSTENITIC HEAT RESISTANT STEEL EXCELLENT IN CREEP RESISTANCE AFTER AGING |
| CN105200338A (en) * | 2014-05-30 | 2015-12-30 | 中国石油化工股份有限公司 | Anti-coking alloy material and use thereof |
| CN107326217A (en) * | 2017-06-27 | 2017-11-07 | 西北工业大学 | A kind of ni-fe-based alloy of high-carbon containing niobium and preparation method |
| CN108130492A (en) * | 2017-12-03 | 2018-06-08 | 江苏长友特钢机械有限公司 | Overhang roll and its manufacturing method |
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