JP2005144488A - Build-up welding material for continuous casting roll and roll using it - Google Patents
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- 238000009749 continuous casting Methods 0.000 title claims abstract description 32
- 239000000463 material Substances 0.000 title claims abstract description 24
- 238000003466 welding Methods 0.000 title claims abstract description 21
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 238000005728 strengthening Methods 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 abstract description 5
- 229910052719 titanium Inorganic materials 0.000 abstract description 4
- 239000000126 substance Substances 0.000 abstract 2
- 229910052748 manganese Inorganic materials 0.000 abstract 1
- 229910052715 tantalum Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 9
- 230000035882 stress Effects 0.000 description 9
- 238000005336 cracking Methods 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 6
- 230000007423 decrease Effects 0.000 description 6
- 229910000601 superalloy Inorganic materials 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 229910000765 intermetallic Inorganic materials 0.000 description 4
- 230000003647 oxidation Effects 0.000 description 4
- 238000007254 oxidation reaction Methods 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 238000000034 method Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical compound F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000009689 gas atomisation Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 238000004227 thermal cracking Methods 0.000 description 1
Abstract
Description
本発明は、高温で高耐力、高延性および低熱膨張特性を有する耐熱亀裂性に優れた連続鋳造ロール肉盛用溶接材料およびロールに関するものである。 The present invention relates to a continuous casting roll overlay welding material and roll having high heat resistance, high ductility and low thermal expansion characteristics at high temperatures and excellent heat crack resistance.
従来、600℃程度の高温下で使用される連続鋳造用ロールは、急過熱と急冷却が繰り返される過酷な使用環境にあり、熱亀裂や高温酸化といった損傷を受け、これらの維持、交換による製造コストアップが課題になっている。これらの課題に対し、例えば特開2001−340991号公報(特許文献1)に開示されているように、耐熱亀裂性に優れた連続鋳造用ロールとして、C:0.07%以下、Si:1%以下、Mn:1%以下、P:0.03%以下、S:0.03%以下、Ni:3〜5%、Cr:15.5〜17.5%、Cu:3〜5%、Mo:1.5%以下、Nb:0.3〜0.6%、残部Feおよび不可避的不純物からなる肉盛層を溶接により形成した連続鋳造用ロールが提案されている。 Conventionally, continuous casting rolls used at a high temperature of about 600 ° C. are in a harsh environment where rapid superheating and rapid cooling are repeated. They are damaged by thermal cracking and high temperature oxidation, and manufactured by maintaining and replacing them. Cost increase is an issue. To solve these problems, for example, as disclosed in Japanese Patent Application Laid-Open No. 2001-340991 (Patent Document 1), as a continuous casting roll having excellent heat cracking resistance, C: 0.07% or less, Si: 1 %: Mn: 1% or less, P: 0.03% or less, S: 0.03% or less, Ni: 3 to 5%, Cr: 15.5 to 17.5%, Cu: 3 to 5%, There has been proposed a continuous casting roll in which a built-up layer composed of Mo: 1.5% or less, Nb: 0.3 to 0.6%, the balance Fe and inevitable impurities is formed by welding.
また、Ni基の耐熱亀裂性に優れた連続鋳造用ロールとして、特開2002−239697号公報(特許文献2)に開示されているように、C:0.05%以下、Si:0.05%以下、Mn:0.2%以下、Cr:17〜22%、Co:10〜14%、Mo:4〜8%、W:0.8〜1.5%、Al+Ti:3〜5.5%、残部Niおよび不可避的不純物からなるNi基合金系粉末を粉体プラズマアーク肉盛溶接方法により厚さ2mm以上肉盛溶接した連続鋳造用肉盛ロールが提案されている。
上述した特許文献1のような、Fe基マルテンサイト系析出硬化型ステンレス鋼や特許文献2のようなNi基オーステナイト系合金を表面に肉盛した連続鋳造用ロールが提案されているが、しかしながら、Fe基ステンレス鋼はNi基超合金と比較して高温耐力に劣り、Ni基超合金は熱膨張係数が比較的大きい。従って、高温耐力、低熱膨張特性を有し、さらに鋳造技術の高速化や高温化などにより、益々連続鋳造用ロールにかかる負荷は増大する傾向から、さらに耐熱亀裂性に優れた材料が求められている。 As described above, a continuous casting roll in which a Ni-based austenitic alloy such as Fe-based martensite precipitation hardening stainless steel or Patent Document 2 is built up on the surface has been proposed. Fe-based stainless steel is inferior in high-temperature yield strength compared to Ni-based superalloys, and Ni-based superalloys have a relatively large thermal expansion coefficient. Therefore, there is a demand for a material having high-temperature proof stress and low thermal expansion characteristics, and more excellent heat-resistant crack resistance because the load applied to the continuous casting roll tends to increase as the casting technology increases in speed and temperature. Yes.
このような使用環境にある連続鋳造用ロールにおける耐熱亀裂性の改善には、高温耐力、高温延性に優れ、かつ低熱膨張特性を有していることが重要である。そこで、上述したように、Fe基ステンレスは一般的にNi基超合金と比較し高温耐力が低く、一方、Ni基超合金は熱膨張係数が比較的高く、これらの材料では耐熱亀裂性が十分でない。 In order to improve the thermal crack resistance of the continuous casting roll in such a use environment, it is important to have excellent high temperature proof stress and high temperature ductility and low thermal expansion characteristics. Therefore, as described above, Fe-based stainless steels generally have lower high-temperature proof stress than Ni-based superalloys, while Ni-based superalloys have a relatively high coefficient of thermal expansion, and these materials have sufficient heat cracking resistance. Not.
而して、Ni基超合金は各種市販されているが、これらは主にガスタービンおよびその周辺用材料として開発されており、1000℃近い温度域での使用を前提に開発されているものが多いため、連続鋳造用ロールの使用温度である600℃前後での使用を前提に開発されたものでないことが多い。また、これら合金は一般的に凝固偏折や異相生成を解消するため1100℃近い温度で固溶化処理された後、700℃程度の温度で時効処理し使用されることが多い。 Thus, although various Ni-base superalloys are commercially available, these are mainly developed as gas turbines and their peripheral materials, and are developed on the assumption that they are used in a temperature range close to 1000 ° C. Therefore, it is often not developed on the premise that the continuous casting roll is used at around 600 ° C. In general, these alloys are often used after being subjected to a solution treatment at a temperature close to 1100 ° C. in order to eliminate solidification bending and heterogeneous phase formation, and then subjected to an aging treatment at a temperature of about 700 ° C.
しかしながら、連続鋳造用として肉盛りされたクラッドロールにおいては、界面割れ等の問題もあり、固溶化処理が困難であるために、固溶化処理を省略した工程においても良好な特性を有することが重要となる。そこで、これらの要素を考慮し鋭意開発を進め、使用温度が600℃前後で、固溶化処理を省略した工程においても脆性相の生成を抑制し、高耐力、高延性、低熱膨張特性を有し、熱間耐摩耗性および耐熱亀裂性に優れたNi基超合金を開発し発明に至ったものである。 However, clad rolls built for continuous casting also have problems such as interfacial cracking, and it is difficult to make a solution treatment, so it is important to have good characteristics even in a process in which the solution treatment is omitted. It becomes. Therefore, in consideration of these factors, the development is advanced and the use temperature is around 600 ° C., and even in the process where the solution treatment is omitted, the formation of the brittle phase is suppressed, and it has high yield strength, high ductility, and low thermal expansion characteristics. The present inventors have developed a Ni-base superalloy excellent in hot wear resistance and heat cracking resistance and led to the invention.
その発明の要旨とするとろは、
(1)質量%で、C:0.1%以下、Cr:10〜15%、Mo:8〜15%、Co:15%以下、W:5%以下、Al:1〜5%、Ti:1〜5%を含み、残部Niおよび不可避的不純物からなり、かつ、Cr%/33+Mo%/25+W%/31≦1を満たすことを特徴とする連続鋳造ロール肉盛用溶接材料。
(2)質量%で、Si:0.5%以下、Mn:0.5%以下を含む前記(1)に記載の連続鋳造ロール肉盛用溶接材料。
The gist of the invention is that
(1) By mass%, C: 0.1% or less, Cr: 10-15%, Mo: 8-15%, Co: 15% or less, W: 5% or less, Al: 1-5%, Ti: A welding material for overlaying continuous casting rolls, comprising 1 to 5%, consisting of the balance Ni and inevitable impurities, and satisfying Cr% / 33 + Mo% / 25 + W% / 31 ≦ 1.
(2) The welding material for continuous casting roll build-up according to the above (1) containing, by mass%, Si: 0.5% or less and Mn: 0.5% or less.
(3)質量%で、S:0.005%以下とした前記(1)または(2)に記載の連続鋳造ロール肉盛用溶接材料。
(4)質量%で、Nb:3%以下、Ta:6%以下を含む前記(1)〜(3)に記載の連続鋳造ロール肉盛用溶接材料。
(3) The welding material for continuous casting roll build-up according to (1) or (2), wherein S is 0.005% or less in mass%.
(4) The welding material for overlaying continuous casting rolls according to the above (1) to (3), which contains, by mass%, Nb: 3% or less and Ta: 6% or less.
(5)20%≦γ´量≦35%、LM絶対値≦0.015Å、Nv,Nv´≦2.30を満たす前記(1)〜(4)に記載の連続鋳造ロール肉盛用溶接材料。
ただし、γ´:Ni3 Alを主とした強化相
LM絶対値:γ−γ´相の格子定数ミスマッチ(Lattice Mismatc h)
Nv:γ相の平均電子空孔数
Nv´:γ´相の平均電子空孔数
(6)前記(1)〜(5)に記載の連続鋳造ロール肉盛用溶接材料を用いてなることを特徴とする連続鋳造ロールにある。
(5) Welding material for continuous casting roll build-up according to (1) to (4) that satisfies 20% ≦ γ ′ amount ≦ 35%, LM absolute value ≦ 0.015 mm, Nv, Nv ′ ≦ 2.30 .
However, strengthening phase mainly composed of γ ′: Ni 3 Al LM absolute value: lattice constant mismatch of γ-γ ′ phase (Lattice Mismatch h)
Nv: average electron vacancy number of γ phase
Nv ′: Average number of electron vacancies of γ ′ phase (6) A continuous casting roll comprising the welding material for overlaying a continuous casting roll according to (1) to (5).
本発明により、高温で高耐力、高延性、低熱膨張特性を有し、かつ、耐熱亀裂性に優れた連続鋳造ロール肉盛用溶接材料およびそれを用いた連続鋳造ロールを得ることが出来る極めて優れた効果を奏するものである。 According to the present invention, it is possible to obtain a continuous casting roll overlay welding material having high proof stress, high ductility, low thermal expansion characteristics at high temperatures and excellent heat cracking resistance, and a continuous casting roll using the same. It is effective.
以下、発明に係る成分組成の限定理由について説明する。
C:0.1%以下
Cは、結晶粒界にTi,Cr,Mo,W等と炭化物を形成し粒界強化するための元素である。しかし、0.1%を超えると粒内のTi,Cr,Mo,W濃度が低下し、耐力、耐酸化性に悪影響を及ぼすことから、その上限を0.1%とした。
Cr:10〜15%
Crは、高温(600℃前後)における耐酸化性を確保するため10%以上の添加が必要である。しかし、15%を超えると脆性な金属間化合物が析出し延性が低下する。従って、その範囲を10〜15%とした。
Hereinafter, the reasons for limiting the component composition according to the invention will be described.
C: 0.1% or less C is an element for strengthening grain boundaries by forming carbides such as Ti, Cr, Mo, and W at grain boundaries. However, if it exceeds 0.1%, the Ti, Cr, Mo, W concentration in the grains decreases, and the proof stress and oxidation resistance are adversely affected, so the upper limit was made 0.1%.
Cr: 10-15%
Cr needs to be added in an amount of 10% or more in order to ensure oxidation resistance at high temperatures (around 600 ° C.). However, if it exceeds 15%, a brittle intermetallic compound is precipitated and ductility is lowered. Therefore, the range was made 10 to 15%.
Mo:8〜15%
Moは、γ相中に固溶し高温耐力を向上する効果、および熱膨張係数を低くする効果を持つ元素である。また、モールドパウダーに含まれるフッ酸に対する耐食性を高める効果もある。しかし、8%未満ではその効果が十分でなく、15%を超える添加は、脆性な金属間化合物が析出し延性が低下することから、その範囲を8〜15%とした。
Co:15%以下
Coは、延性を改善する効果のある元素である。しかし、15%を超えるとコストアップとなることから、その上限を15%とした。
Mo: 8-15%
Mo is an element having the effect of improving the high-temperature proof stress by dissolving in the γ phase and lowering the thermal expansion coefficient. In addition, there is an effect of increasing the corrosion resistance against hydrofluoric acid contained in the mold powder. However, if the amount is less than 8%, the effect is not sufficient, and if it exceeds 15%, a brittle intermetallic compound is precipitated and the ductility is lowered, so the range was made 8 to 15%.
Co: 15% or less Co is an element having an effect of improving ductility. However, if it exceeds 15%, the cost increases, so the upper limit was made 15%.
W:5%以下
Wは、γ相中に固溶し高温耐力を向上する効果、および熱膨張係数を低くする効果を持つ元素である。しかし、5%を超える添加は、脆性な金属間化合物が析出し延性が低下することから、その上限を5%とした。
Al:1〜5%
Alは、γ´相を形成し高温耐力を向上させる効果を有する。しかし、1%未満ではその効果は十分でなく、また、5%を超えると延性が低下することから、その範囲を1〜5%とした。
W: 5% or less W is an element having an effect of improving the high temperature proof stress by dissolving in the γ phase and an effect of lowering the thermal expansion coefficient. However, if over 5% is added, brittle intermetallic compounds are precipitated and ductility is lowered, so the upper limit was made 5%.
Al: 1 to 5%
Al has the effect of forming a γ ′ phase and improving high-temperature yield strength. However, if it is less than 1%, the effect is not sufficient, and if it exceeds 5%, the ductility decreases, so the range was made 1 to 5%.
Ti:1〜5%
Tiは、γ´相中のAlと置換しγ´相を強化する。しかし、1%未満ではその効果が十分でなく、5%を超えると延性が低下することから、その範囲を1〜5%とした。
Cr%/33+Mo%/25+W%/31≦1
Cr%/33+Mo%/25+W%/31の値が1を超えると脆性な金属間化合物が生成し延性が低下することから、その上限を1とした。
Ti: 1 to 5%
Ti replaces Al in the γ ′ phase and strengthens the γ ′ phase. However, if it is less than 1%, the effect is not sufficient, and if it exceeds 5%, the ductility decreases, so the range was made 1 to 5%.
Cr% / 33 + Mo% / 25 + W% / 31 ≦ 1
When the value of Cr% / 33 + Mo% / 25 + W% / 31 exceeds 1, brittle intermetallic compounds are formed and ductility is lowered, so the upper limit was set to 1.
Si:0.5%以下
Siは、肉盛時の湯流れ性を良くするための元素である。しかし、0.5%を超えると酸化物等の介在物が析出し衝撃値等の機械特性を低下させる。従って、その上限を0.5%とした。
Mn:0.5%以下
Mnは、Siと同様に、肉盛時の湯流れ性を良くするための元素である。しかし、0.5%を超えると酸化物等の介在物が析出し衝撃値等の機械特性を低下させる。従って、その上限を0.5%とした。
Si: 0.5% or less Si is an element for improving the hot-water flow when building up. However, if it exceeds 0.5%, inclusions such as oxides are precipitated, and mechanical properties such as impact value are deteriorated. Therefore, the upper limit was made 0.5%.
Mn: 0.5% or less Mn is an element for improving the flowability of hot water during overlaying, like Si. However, if it exceeds 0.5%, inclusions such as oxides are precipitated, and mechanical properties such as impact value are deteriorated. Therefore, the upper limit was made 0.5%.
S:0.005%以下
Sは、肉盛時の高温割れに起因する元素である。従って、肉盛時の高温割れを抑制するためには、0.005%以下にする必要がある。
Nb:3%以下
Nbは、γ´相中に固溶し耐力を向上させる元素である。しかし、3%を超えると延性が低下することから、その上限を3%とした。
Ta:6%以下
Taは、Nbと同様に、γ´相中に固溶し耐力を向上させる元素である。しかし、6%を超えると延性が低下することから、その上限を6%とした。
S: 0.005% or less S is an element resulting from hot cracking during overlaying. Therefore, in order to suppress the high temperature crack at the time of overlaying, it is necessary to make it 0.005% or less.
Nb: 3% or less Nb is an element that improves the yield strength by solid solution in the γ ′ phase. However, if it exceeds 3%, the ductility decreases, so the upper limit was made 3%.
Ta: 6% or less Ta, like Nb, is an element that dissolves in the γ ′ phase and improves the yield strength. However, if it exceeds 6%, the ductility decreases, so the upper limit was made 6%.
20%≦γ´量≦35%、LM絶対値≦0.015Å、Nv,Nv´≦2.30
γ´量は、20%未満では耐力が低く、35%を超えると延性が低くなり、また、肉盛割れが発生しやすくなることから、その範囲を20〜35%とした。好ましくは、23〜30%とする。LM絶対値は、0.015Åを超えるとγ´相が凝集して析出し延性が低下する。従って、その上限を0.015Åとした。好ましくは0.010Åとする。Nv,Nv´は、2.30を超えると脆性相が析出し延性が低下する。従って、その上限を2.30とした。好ましくは2.28とする。
20% ≦ γ ′ amount ≦ 35%, LM absolute value ≦ 0.015Å, Nv, Nv ′ ≦ 2.30
If the amount of γ ′ is less than 20%, the yield strength is low, and if it exceeds 35%, the ductility becomes low, and build-up cracking is likely to occur. Therefore, the range is set to 20 to 35%. Preferably, it is 23 to 30%. When the LM absolute value exceeds 0.015%, the γ 'phase aggregates and precipitates, and ductility decreases. Therefore, the upper limit was set to 0.015cm. Preferably it is 0.010 mm. When Nv and Nv ′ exceed 2.30, a brittle phase is precipitated and ductility is lowered. Therefore, the upper limit was set to 2.30. Preferably it is 2.28.
なお、上述したLM絶対値は、γ−γ´相の格子定数ミスマッチ(Lattice Mismatch)を表し、また、Nv、Nv´は、それぞれγおよびγ´の平均電子空孔数であって、Nv=ΣCxNx、およびNv´=ΣC´xNx、によって表される。ここで、CxおよびC´xは、それぞれγおよびγ´相を構成するX元素の濃度であり、Nxは、X元素の固有電子空孔数である。 The LM absolute value described above represents a lattice constant mismatch of the γ-γ ′ phase, and Nv and Nv ′ are the average electron vacancy numbers of γ and γ ′, respectively, and Nv = ΣCxNx and Nv ′ = ΣC′xNx. Here, Cx and C′x are the concentrations of the X element constituting the γ and γ ′ phases, respectively, and Nx is the number of intrinsic electron vacancies of the X element.
この平均電子空孔数とは、Ni基合金において、γマトリックス中にγ´が均一に析出したγとγ´相合金と限定した場合に、γとγ´組成は合金元素含有量がγおよびγ´の固溶度を超えない範囲内に限定される。この限界を超えるとかりに当初はγおよびγ´相だけであっても、長時間使用中にγおよびγ´相の他にσ相などの相を析出したり、あるいはγ´相がη相またはδ相に変態して性質を劣化させる。この限界を規定する量の一つがこの平均電子空孔数である。NvおよびNv´が2.26以下であれば、σ相は全く生成せず、2.41を超えると常にσ相が生成し、この中間ではσ相が生成する場合としない場合の両方がある。従って、平均電子空孔数は、γあるいはγ´とσ相の境界を限定する量とみることが出来る。 The average number of electron vacancies in a Ni-based alloy is limited to γ and γ ′ phase alloys in which γ ′ is uniformly precipitated in the γ matrix. It is limited within a range not exceeding the solid solubility of γ ′. Even if it is only γ and γ ′ phases at the beginning when this limit is exceeded, a phase such as σ phase is precipitated in addition to γ and γ ′ phases during use for a long time, or γ ′ phase is η phase or It transforms into δ phase and deteriorates its properties. One of the quantities defining this limit is the average number of electron vacancies. If Nv and Nv ′ are 2.26 or less, the σ phase is not generated at all, and if it exceeds 2.41, the σ phase is always generated, and there are cases where the σ phase is generated or not in the middle. . Therefore, the average number of electron vacancies can be regarded as an amount that limits the boundary between γ or γ ′ and the σ phase.
以下、本発明について実施例によって具体的に説明する。
25kgの母材をAr雰囲気中にて誘導溶解炉にて溶解し、φ5のノズルから1600℃にて出湯し、Arガスでガスアトマイズし、表1に示すような成分組成の粉末を得た。これを−250/+63μmに分級し、低合金基材に6層のPTA肉盛した。この肉盛層より引張試験片、熱膨張試験片を作製し、600℃−4時間の熱処理を行なった。その結果を表1に示す。その評価として、0.2%耐力(MPa)および伸び(%)は600℃の引張試験を行い、また、熱膨張係数(×10-6)はRT〜600℃での熱膨張特性として示す。
Hereinafter, the present invention will be specifically described with reference to examples.
A 25 kg base material was melted in an induction melting furnace in an Ar atmosphere, hot water was discharged from a φ5 nozzle at 1600 ° C., and gas atomization was performed with Ar gas to obtain a powder having a component composition as shown in Table 1. This was classified to −250 / + 63 μm, and 6 layers of PTA were deposited on the low alloy substrate. A tensile test piece and a thermal expansion test piece were prepared from this build-up layer and heat-treated at 600 ° C. for 4 hours. The results are shown in Table 1. As the evaluation, 0.2% proof stress (MPa) and elongation (%) are subjected to a tensile test at 600 ° C., and the thermal expansion coefficient (× 10 −6 ) is shown as thermal expansion characteristics at RT to 600 ° C.
表1に示すように、No.1〜10は本発明例であり、No.11〜15は比較例である。比較例No.11は成分組成であるMo量が低いために、0.2%耐力が低い。比較例No.12はCr量が高く、Mo量が低いために、0.2%耐力が低く、熱膨張係数が高い。比較例No.13はC量が高く、Cr量が低く、Tiが高いために、伸びおよび耐酸化性に劣る。比較例No.14はC量が高く、W量が高く、S量も高いために、耐力および伸びが悪い。比較例No.15はMo量が高く、Tiが低く、Siが高いために、0.2%耐力および伸びに劣る。これに対し、本発明例であるNo.1〜10の何れにおいても優れていることが分かる。
特許出願人 山陽特殊製鋼株式会社 他1
代理人 弁理士 椎 名 彊
As shown in Table 1, no. 1 to 10 are examples of the present invention. 11 to 15 are comparative examples. Comparative Example No. No. 11 has a low 0.2% yield strength because the amount of Mo as a component composition is low. Comparative Example No. Since No. 12 has a high Cr content and a low Mo content, it has a low 0.2% yield strength and a high thermal expansion coefficient. Comparative Example No. No. 13 has a high C content, a low Cr content, and a high Ti content, and therefore is inferior in elongation and oxidation resistance. Comparative Example No. No. 14 has a high C content, a high W content, and a high S content. Comparative Example No. No. 15 has a high Mo content, low Ti, and high Si, and therefore is inferior in 0.2% proof stress and elongation. In contrast to this, No. It turns out that it is excellent in any of 1-10.
Patent applicant Sanyo Special Steel Co., Ltd. and others 1
Attorney: Attorney Shiina
Claims (6)
C:0.1%以下、
Cr:10〜15%、
Mo:8〜15%、
Co:15%以下、
W:5%以下、
Al:1〜5%、
Ti:1〜5%、
を含み、残部Niおよび不可避的不純物からなり、かつ、Cr%/33+Mo%/25+W%/31≦1を満たすことを特徴とする連続鋳造ロール肉盛用溶接材料。 % By mass
C: 0.1% or less,
Cr: 10 to 15%,
Mo: 8-15%,
Co: 15% or less,
W: 5% or less,
Al: 1 to 5%,
Ti: 1 to 5%,
A continuous casting roll overlay welding material characterized by comprising the balance Ni and unavoidable impurities and satisfying Cr% / 33 + Mo% / 25 + W% / 31 ≦ 1.
ただし、γ´:Ni3 Alを主とした強化相
LM絶対値:γ−γ´相の格子定数ミスマッチ
Nv:γ相の平均電子空孔数
Nv´:γ´相の平均電子空孔数 The continuous casting roll overlay welding material according to claim 1, satisfying 20 ≦ γ ′ amount ≦ 35%, LM absolute value ≦ 0.015%, Nv, Nv ′ ≦ 2.30.
However, strengthening phase mainly composed of γ ′: Ni 3 Al LM absolute value: lattice constant mismatch of γ-γ ′ phase
Nv: average electron vacancy number of γ phase
Nv ′: average number of electron vacancies in the γ ′ phase
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Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
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JP2006255767A (en) * | 2005-03-18 | 2006-09-28 | Sanyo Special Steel Co Ltd | Ni-RADICAL BUILDING UP POWDER FOR DIE USED IN HOT WORKING AND DIE FOR HOT WORKING |
JP2007136509A (en) * | 2005-11-18 | 2007-06-07 | Sanyo Special Steel Co Ltd | Build-up welding material for continuous casting roll, and roll |
JP2011052688A (en) * | 2009-08-31 | 2011-03-17 | General Electric Co <Ge> | Process and alloy for turbine blade and the blade formed by using them |
CN111471898A (en) * | 2020-05-08 | 2020-07-31 | 华能国际电力股份有限公司 | Low-expansion high-temperature alloy and preparation process thereof |
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2003
- 2003-11-14 JP JP2003384496A patent/JP4439881B2/en not_active Expired - Lifetime
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
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JP2006255767A (en) * | 2005-03-18 | 2006-09-28 | Sanyo Special Steel Co Ltd | Ni-RADICAL BUILDING UP POWDER FOR DIE USED IN HOT WORKING AND DIE FOR HOT WORKING |
JP4679942B2 (en) * | 2005-03-18 | 2011-05-11 | 山陽特殊製鋼株式会社 | Ni-based overlaying powder for molds used hot and hot molds |
JP2007136509A (en) * | 2005-11-18 | 2007-06-07 | Sanyo Special Steel Co Ltd | Build-up welding material for continuous casting roll, and roll |
JP2011052688A (en) * | 2009-08-31 | 2011-03-17 | General Electric Co <Ge> | Process and alloy for turbine blade and the blade formed by using them |
CN111471898A (en) * | 2020-05-08 | 2020-07-31 | 华能国际电力股份有限公司 | Low-expansion high-temperature alloy and preparation process thereof |
CN111471898B (en) * | 2020-05-08 | 2021-03-30 | 华能国际电力股份有限公司 | Low-expansion high-temperature alloy and preparation process thereof |
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