JPH05239576A - Nickel-base heat resistant alloy excellent in workability - Google Patents

Abstract

PURPOSE:To obtain a nickel-base heat resistant alloy usable for members with high temp. strength and having superior hot workability, high temp. strength, and high corrosion resistance. CONSTITUTION:This alloy is a nickel-base heat resistant alloy having a composition consisting of, by weight, <=0.10% C, <=1.0% Si, <=0.2% Mn, <=5% Cr, 5.5-12% Al, >5-20% Fe, further one or more kinds among 0.001-0.03% B, 0.01-0.3% Zr, 0.05-1.0% Hf, 0.05-1.0% Ti, and 0.001-0.02% Mg, and the balance Ni with inevitable impurities, excellent in workability, and having superior high temp. strength and corrosion resistance. Besides the above components, one or more elements selected from the group consisting of 0.5-5% Mo and 1.0-10% W, the group consisting of 0.3-3% V, 0.5-5% Nb, and 1.0-10% Ta, and the group consisting of 0.01-0.25% Y, 0.01-0.25% La, and 0.01-0.25% Ce can further be incorporated.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION This invention has high strength at high temperature and excellent corrosion resistance. In particular, it decomposes raw materials such as naphtha, propane, ethane, and gas oil with steam at a high temperature of 800 ° C. The present invention relates to a nickel-base heat-resistant alloy suitable as a raw material for a pipe used for producing a product, that is, a cracking furnace pipe for an ethylene plant.

[0002]

2. Description of the Related Art With respect to the operating conditions of cracking furnace tubes for ethylene plants, with the recent increase in demand for synthetic resins, there is a strong tendency toward higher temperatures from the viewpoint of improving ethylene yield. Since the inner surface of such a cracking furnace tube is exposed to a carburizing atmosphere, a heat resistant material excellent in high temperature strength and carburizing resistance is required. On the other hand, during operation, carbon is precipitated on the inner surface of the cracking furnace tube (this phenomenon is called coking), and as the amount of precipitation increases, there are adverse effects on operation such as an increase in ΔP and a decrease in heating efficiency. Therefore, in actual operation, so-called decoking work is regularly performed to remove carbon deposited by air or steam, but during that time, there are serious problems such as operation stoppage and man-hours of work. Such caulking and the problems associated therewith become more serious as the size of the cracking furnace tube becomes smaller, which is advantageous for improving the yield.

[0003] formed as a prior art for the purpose of preventing coking, for example in JP-A-2-8336, a strong, stable Cr ₂ 0 ₃ coating on the alloy surface by incorporating 28% or more Cr in the alloy It has been proposed to prevent Fe and Ni, which are catalytic elements that promote carbon deposition, from floating on the surface of the tube and suppress coking.

On the other hand, in order to improve the carburization resistance, it is known that increasing the Si content in the alloy is effective, as disclosed in, for example, Japanese Patent Laid-Open No. 23050/1982. ..

However, the above-mentioned conventional technique still has the following problems.

When a high Cr alloy as disclosed in Japanese Patent Laid-Open No. 2-8336 is applied as a high temperature strength member from the viewpoint of preventing coking, the amount of Ni in the alloy is increased to austenite the metal structure. Although it is necessary, the high temperature strength is lower than conventional alloys, and it is difficult to use this high Cr alloy alone as a high temperature strength member. Therefore, this Japanese Patent Laid-Open No. 2-8336
In the invention of the publication, the double pipe is used in combination with other high-strength material, but the double pipe has a high manufacturing cost, and there are many problems in terms of economical efficiency and reliability.

The inventors of the present invention can improve carburization resistance and coking resistance as compared with conventional alloys by increasing the amount of Al in the alloy and forming a strong and dense Al ₂ O ₃ film on the metal surface. Moreover, in such a high Al alloy, by increasing the amount of Ni, the γ'phase was finely precipitated in the matrix during use at high temperature, and the creep rupture strength was also improved. Filed as No. 3-61821.

However, the alloy of the invention of Japanese Patent Application No. 3-61821 attaches great importance to high temperature strength, so that it cannot always be said that workability is good.

[0009]

The present invention is excellent in high-temperature strength and corrosion resistance, and particularly excellent in pyrolysis and thermal cycle environments in which carburization, oxidation and temperature fluctuations are repeated, such as in a cracking furnace tube for an ethylene plant. An object of the present invention is to provide a heat-resistant alloy having carburization resistance and coking resistance, creep rupture strength sufficient for use as a high-temperature strength member, and excellent workability.

[0010]

The gist of the present invention resides in the following nickel-base heat-resistant alloy. All% relating to the content of alloy components mean% by weight.

(1) C: 0.10% or less, Si: 1.0% by weight
Below, Mn: 0.2% or less, Cr: 5% or less, Al: 5.5-12%,
Fe: more than 5% and up to 20%, further B: 0.001 to 0.
03%, Zr: 0.01 to 0.3%, Hf: 0.05 to 1.0%, Ti: 0.05
~ 1.0% and Mg: 0.001 to 0.02%, and the balance is Ni and inevitable impurities. Nickel base heat resistant alloy with excellent workability and high temperature strength and corrosion resistance.

(2) In addition to the above component (1), Mo: 0.5
~ 5% and W: 1.0 to 10%, a nickel-base heat-resistant alloy with excellent high-temperature strength and corrosion resistance, which has excellent workability and contains one or two kinds.

(3) In addition to the above component (1) or (2), it further contains at least one of V: 0.3 to 3%, Nb: 0.5 to 5% and Ta: 1.0 to 10%. A nickel-base heat-resistant alloy with excellent workability and high-temperature strength and good corrosion resistance.

(4) In addition to the above component (1), (2) or (3), Y: 0.01 to 0.25%, La: 0.01 to 0.25% and
Ce: A nickel-base heat-resistant alloy containing at least one of 0.01 to 0.25% and having excellent workability, high temperature strength, and good corrosion resistance.

When particularly high strength is required, the C content of the alloys (1) to (4) exceeds 0.02%,
It is recommended to select the range up to 0.10%.

[0016]

[Operation] As described above, high Si content is required to improve the carburization resistance of the alloy.
It is known that it is effective to form a SiO ₂ film at the metal / scale interface by chemical conversion. On the other hand, in order to improve coking resistance, by increasing the Cr, the outermost oxide scale surface
It is also known that it is effective to form a film of Cr ₂ O ₃ .

The inventors of the present invention also conducted research on the idea that formation of a strong and dense surface oxide film is effective for improving carburization resistance and coking resistance. As a result, by increasing the Al content in the alloy to form a strong and dense Al ₂ O ₃ film uniformly on the metal surface, the carburization resistance and coking resistance are significantly higher than those of conventional alloys. It has been found to improve. Furthermore, in such high Al alloys, Ni
By increasing the amount, the γ'phase is finely precipitated in the matrix during use at high temperature, and the creep rupture strength is also greatly improved. Therefore, the alloy based on Ni and having a higher Al content becomes a heat-resistant alloy having both corrosion resistance and high-temperature strength, and is suitable for the above-mentioned applications as a high-temperature strength member. Is not always good. As a result of further research on workability improvement, the present inventors have found that the addition of an appropriate amount of Fe slightly improves the high-temperature strength but significantly improves the workability.

Hereinafter, the function and effect of the components constituting the alloy of the present invention and the proper content thereof will be described.

C: It is an effective element for forming carbides and improving the tensile strength and creep rupture strength required for heat resistant steel, but if the content exceeds 0.10%, the ductility and toughness of the alloy decrease. growing. In particular, when importance is attached to ductility and toughness, it is desirable to control C to 0.02% or less. On the other hand, 0.02% when stressing creep rupture strength
It is preferable to contain C up to 0.10% to finely disperse a relatively large amount of carbide.

Si: an element required as a deoxidizing element, which contributes to the improvement of oxidation resistance and carburization resistance, but its effect is relatively small in high Al alloys such as the alloy of the present invention.
If Si is present excessively, carbides will be nonuniformly precipitated and mechanical properties such as toughness will be deteriorated, so Si was made 1.0% or less.

Mn: Mn is an element effective as a deoxidizing element, but its content is 0.2 because it promotes the formation of a spinel type oxide film which causes deterioration of coking resistance.
It is necessary to keep the percentage below.

Cr: Cr is an element effective in improving the oxidation resistance and the coking resistance, but it is not necessary to add a large amount in an alloy having a high Al content such as the alloy of the present invention. Further, when Cr is contained in excess, carbides are nonuniformly precipitated as in the case of excessive Si, and mechanical properties such as toughness are deteriorated. Therefore, in the present invention, the Cr content is 5% or less.

Al: Al is an extremely effective element for improving carburization resistance and coking resistance, but in order to exert its effect, it is necessary to uniformly form a corundum type Al ₂ O ₃ oxide film. is there. For that, at least 5.5%
Al is required. However, when Al exceeds 12.0%, ductility and toughness at room temperature and high temperature are significantly deteriorated, and it cannot be used as a high temperature strength member. Therefore, the proper content of Al is 5.5 to 12.0%. By including Al in this range, the γ'phase is finely precipitated during use, and the creep rupture strength is also improved.

B, Zr, Hf, Ti and Mg: These elements are mainly effective for strengthening the grain boundaries of the alloy. In order to exert their effects, B is 0.001% or more and Zr is 0.01%.
Above, Hf 0.05% or more, Ti 0.05% or more, Mg 0.001%
Above, each is required. However, if the content is excessive, the creep rupture strength decreases again, so the upper limit is B.
0.03%, Zr 0.3%, Hf 1.0%, Ti 1.0%, Mg 0.0
2% These elements may be contained alone or in combination of two or more.

Fe: Fe is a component that contributes to improving the hot workability of nickel-base high Al alloys such as the alloys of the present invention. In order to exert its effect, an amount exceeding at least 5% is necessary, and the hot workability improves as the content increases.
However, if it exceeds 20%, the amount of undissolved β phase increases, the growth of austenite crystal grains is suppressed, and the creep rupture strength sharply decreases. Therefore, the proper range of Fe exceeds 5%
Up to 20%.

One of the alloys of the present invention is Ni, with the balance being Ni, in addition to the above components. Ni is an element that is indispensable for obtaining a stable austenite structure and ensuring the carburization resistance. Particularly, it is more preferable for increasing the effect of precipitation strengthening by the γ'phase. However, since the workability deteriorates, the nickel-based alloy containing an appropriate amount of Fe was selected in the present invention.

The alloy of the present invention may further contain the following components in addition to the above components.

Mo and W: Mo and W are mainly effective as solid solution strengthening elements, and increase the creep rupture strength by strengthening the austenite phase of the matrix. In order to exert this effect, Mo is 0.5% or more and W is 1.0%.
The above is required. However, if it is contained excessively, not only the intermetallic compound that causes the toughness decrease precipitates but also the carburization resistance and coking resistance deteriorate, so Mo is up to 5% and W is up to 10%.
Should be suppressed by. When two kinds of these are used together, the total content of Mo + (1/2) W should be suppressed to 5% or less.

V, Nb and Ta: These elements form a solid solution in the austenite phase as well as in the γ'phase and Cr carbide, and contribute to the improvement of creep rupture strength. In order to exert its effect, V is 0.3% or more and Nb is 0.5%.
As described above, Ta must be 1.0% or more, but if it is contained excessively, toughness is deteriorated, so the upper limit is 3% for V, 5% for Nb, and Ta.
To 10%.

When two or more kinds are added in combination, the total content is preferably 5% or less of (5/3) V + Nb + (1/2) Ta.

Y, La and Ce: These elements mainly improve the adhesion of SiO ₂ and (Al, Cr) ₂ O ₃ coatings under thermal cycling conditions and are excellent even when used under temperature fluctuations. Carburization resistance and coking resistance are maintained. In order to exert the effect, each of Y, La and Ce must be 0.01% or more. However, if it is contained excessively, the workability is deteriorated, and the effect of improving the adhesion of the film is saturated, so the upper limits of Y, La and Ce are
0.25% These elements may be contained alone or in combination of two or more.

Further, in the alloy of the present invention, one or more elements are selected from the above three groups of Mo and W, V, Nb and Ta and Y, La and Ce. It may be contained.

The alloy of the present invention is used as a product such as a pipe after being melted in a usual melting and refining process, then cast, as-cast, or further subjected to processing steps such as forging, rolling and extrusion. In addition, you may make it into a product by a powder metallurgy method. The heat treatment promotes the homogenization of the structure and contributes to the performance improvement of the alloy of the present invention. In this case, the homogenizing treatment is usually performed at 1200 to 1300 ° C., but the casting or the processing as it is can be used.

[0034]

[Examples] Tables 1-1 and 1-2 show the chemical compositions of the test materials. No. 1 to No. 32 are alloys of the present invention, A to V are comparative alloys, and W, X and Y are conventional alloys. The alloys of the present invention and comparative alloys were each subjected to solution heat treatment at 1225 ° C. after ingots of 17 kg vacuum high frequency melting were forged into 15 mm plate materials. Conventional alloys W and X were subjected to 50 kg vacuum induction melting, then forged and cold rolled into a plate material having a thickness of 10 mm, and then subjected to solution heat treatment at 1250 ° C. Conventional alloy Y is an as-cast centrifugal casting tube with an outer diameter of 120 mm and a wall thickness of 10 mm.

Using these test materials, carburization resistance, coking resistance, high temperature strength characteristics by creep rupture test and hot workability by greeble test were evaluated. The carburization resistance was evaluated by solid carburizing test method using BaTiO
1150 ℃ × 100h using carburizing agent of ₃ + charcoal (mixing ratio 3: 7)
Was heat-treated, and the average C increase before and after the test was evaluated. The caulking resistance was evaluated by the gas carburizing test method.
A test was conducted at 1050 ° C. for 30 hours in an atmosphere of% CH ₄ + 20% H ₂ O, and the amount of C adhering to the surface of the test piece was evaluated. The high temperature strength property evaluation was performed by a creep rupture test at 1100 ° C. and 1.0 kgf / mm ² . The hot workability was evaluated by the greeble test at a reduction value of 1200 ° C. and a strain rate of 5 / sec. These test results are shown in Table 2-1 to Table 2-2 and FIG.
~ Collectively shown in FIG.

FIG. 1 shows the influence of the Fe content in the alloy on the drawing value, that is, the hot workability, from the results of Tables 2-1 and 2-2. It is a figure shown about reference alloy code A to code F and code V corresponding to these. The symbols in the figure show alloy Nos. And symbols in Tables 1-1 and 1-2. The curves showing the tendency are connected by being stratified by the Al content in the alloy. It can be seen that the hot workability is remarkably improved from the Fe content of 5% and is improved up to 20% with the increase of the Fe content.

FIG. 2 is a diagram showing the effects of the Fe content on the aperture values of the alloys No. 13 to No. 27 of the present invention in comparison with the corresponding comparative alloy symbols G to U, respectively. Also in these invention alloys, it is understood that the hot workability is improved when the Fe content is within the range of the present invention.

On the other hand, as is clear from Tables 2-1 and 2-2, the carburization resistance and coking resistance are remarkably improved as compared with the conventional alloy and have the same performance as the comparative alloy. I understand. This is because by increasing Al in the alloy to 5.5% or more, a strong and dense single-layer corundum type Al ₂ O ₃ oxide film was formed on the metal surface. Further, the formation of such an Al ₂ O ₃ single-layer coating in the range of Al of 5.5% or more is achieved only by suppressing the Mn in the alloy to 0.2% or less.

FIG. 3 shows the invention alloys No. 1 to No. 12 and
It is a figure which similarly shows the relationship between Fe content and creep rupture strength for No. 28 to No. 30 and comparative alloy codes A to F and code V corresponding to these, stratified by Al content. The creep rupture strength shows a tendency to decrease slightly with an increase in the Fe content, and although it may be lower than that of the comparative alloy, it is not so large. When the Fe content is up to 20%, it is significantly higher than the conventional alloys shown in Table 2-2. This is due to the fine precipitation of the γ'phase in the matrix during use at high temperatures.

FIG. 4 shows Fe alloys No. 13 to No. 27 of the present invention and corresponding comparative alloy symbols G to U.
It is a figure which shows the relationship between content and creep rupture strength. As is clear from FIG. 4 and Table 2-2, the creep rupture strength of these alloys of the present invention tends to be lower than that of the comparative alloy when Fe is contained.
It turns out to be expensive.

[0041]

[Table 1-1]

[0042]

[Table 1-2]

[0043]

[Table 2-1]

[0044]

[Table 2-2]

[0045]

The alloy of the present invention is excellent not only in high temperature strength, carburization resistance and coking resistance but also in workability. In particular, it is suitable as a cracking furnace tube for an ethylene plant, and can be used as a single tube without using a double tube.

[Brief description of drawings]

FIG. 1 is a diagram showing the relationship between Fe content and hot workability for some nickel-based alloys of the present invention and comparative alloys.

FIG. 2 is a diagram showing the relationship between the Fe content and hot workability for another part of the nickel-based alloy of the present invention and the comparative alloy.

FIG. 3 is a diagram showing the relationship between the Fe content and the creep rupture time at 1.0 kgf / mm ² at 1100 ° C. for some nickel-based alloys of the present invention and comparative alloys.

FIG. 4 is a diagram showing the relationship between the Fe content and the creep rupture time at 1.0 kgf / mm ² at 1100 ° C. for another part of the nickel-base alloy of the present invention and the comparative alloy.

Claims (5)

[Claims] 1. By weight%, C: 0.10% or less, Si: 1.0% or less, Mn: 0.2% or less, Cr: 5% or less, Al: 5.5-12%, Fe:
Contains more than 5% and up to 20%, and further B: 0.001 to 0.03
%, Zr: 0.01 to 0.3%, Hf: 0.05 to 1.0%, Ti: 0.05 to
A nickel-base heat-resistant alloy that contains 1.0% and Mg: 0.001 to 0.02%, and the balance is Ni and unavoidable impurities, and has excellent workability and high-temperature strength and corrosion resistance. 2. In addition, Mo: 0.5 to 5% and W: 1.0 to 10%
The nickel-base heat-resistant alloy according to claim 1, which is excellent in workability and excellent in high-temperature strength and corrosion resistance. 3. In addition, V: 0.3-3%, Nb: 0.5-5%
And Ta: 1.0 to 10%, at least one of which is a nickel-base heat-resistant alloy excellent in workability and excellent in high-temperature strength and corrosion resistance. 4. Further, in addition, Y: 0.01 to 0.25%, La: 0.01
To 0.25% and Ce: 0.01 to 0.25%, and a nickel-base heat-resistant alloy having excellent high-temperature strength, excellent workability and good corrosion resistance according to any one of claims 1 to 3. 5. A nickel-base heat-resistant alloy having a C content of more than 0.02% and not more than 0.10%, which is excellent in workability and has high temperature strength and corrosion resistance.