CN113265582A - Fe-Ni-Cr-Mo-Cu alloy - Google Patents
Fe-Ni-Cr-Mo-Cu alloy Download PDFInfo
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Abstract
The invention provides an Fe-Ni-Cr-Mo-Cu alloy which can prevent the generation of cracks and prevent the melting loss and the attachment of slag on the upper edge even if cutting is performed by melt cutting. An Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion, which comprises: carbon (C): 0.004 to 0.025 mass%, silicon (Si): 0.02 to 0.60 mass%, manganese (Mn): 0.03 to 0.35 mass%, phosphorus (P): 0.040 mass% or less, sulfur (S): 0.003 mass% or less of nickel (Ni): 30.0 to 40.0 mass%, chromium (Cr): 21.0 to 25.0 mass%, molybdenum (Mo): 6.50 to 8.00 mass%, nitrogen (N): 0.18-0.28 mass%, copper (Cu): 2.50 to 5.00 mass%, aluminum (Al): 0.001 to 0.100 mass%, titanium (Ti): 0.001 to 0.010 mass%, tin (Sn): 0.001 to 0.050% by mass and zinc (Zn): 0.001 to 0.030 mass%, the balance being iron (Fe) and unavoidable impurities.
Description
Technical Field
The present invention relates to an Fe-Ni-Cr-Mo-Cu alloy having excellent cutting characteristics, and more particularly, to an Fe-Ni-Cr-Mo-Cu alloy capable of preventing cracks and melting loss of an upper edge portion after cutting by cutting while melting a material using a laser, plasma, gas, powder, or the like, and preventing adhesion of dross.
Background
Since Fe — Ni — Cr — Mo — Cu alloy has excellent corrosion resistance, it is used in various technical fields such as seawater environment, chemical plants, and flue gas desulfurization devices mounted on ships. On the other hand, in the above-mentioned technical fields, when a general-purpose alloy such as stainless steel such as SUS304 or SUS316 is used, since the corrosion resistance of the general-purpose alloy is insufficient, defects such as general corrosion, crevice corrosion, grain boundary corrosion, etc. occur in the general-purpose alloy, and there are cases where the application in the above-mentioned technical fields is severely restricted. The Fe-Ni-Cr-Mo-Cu alloy exhibits excellent corrosion resistance by adding a large amount of Cr, Mo, and Cu elements.
As an Fe-Ni-Cr-Mo-Cu alloy having excellent corrosion resistance, an austenitic stainless steel containing, in mass%, Fe — Ni — Cr-Mo-Cu (patent document 1) has been proposed
C：0.001～0.100％、
Si：0.01～1.00％、
Mn：0.01～1.00％、
P: less than 0.050%,
S: less than 0.0050%,
Ni：17.00～35.00％、
Cr：18.00～30.00％、
Mo：4.00～8.00％、
Cu：0.10～3.00％、
N: 0.100 to 0.400% and
al: 0.001 to 0.100%, and the balance being Fe and unavoidable impurities, wherein the austenitic stainless steel satisfies the following formula (1).
Fe+1.2×Cr+1.5×Mo-2×Ni-5×Cu≤50.000···(1)。
The austenitic stainless steel disclosed in patent document 1 has excellent corrosion resistance when used for brazed structures such as marine structures and exhaust gas desulfurization devices, and brazed structural members such as exhaust heat recovery devices and exhaust heat exchange members such as EGR coolers, which are automotive members.
On the other hand, the alloy sheet is cut into a predetermined shape and size and used. As a cutting means of the alloy sheet, fusion cutting may be used. The alloy plate cutting by the fusion cutting has the advantage of excellent production efficiency. However, as shown in fig. 3, in the case of a conventional alloy containing a large amount of elements that are easily oxidized, such as Cr and Al, as in patent document 1, when the alloy plate 10 is cut by fusion cutting, a large amount of dross (slag) 1 containing the above-described components may be firmly attached to the lower edge portion 13 of the fusion cut surface 11. In order to remove the adhering dross 1, grinding or sawing by machining is required, which becomes a factor that significantly suppresses productivity. In addition, the melting loss (dent) 2 may occur in the upper edge portion 12 of the melt-cut surface 11. Further, elements such as Cu and Mo significantly improve the corrosion resistance of the alloy, but are also likely to be concentrated in the final solidification portion of the slab after melting. As in patent document 1, the alloy sheet 10 containing a large amount of the above-described elements is likely to have a melt-cut crack in the Cu and Mo concentrated layer at the center of the sheet thickness t. FIG. 3 is an explanatory view showing a melt-sliced surface state of a conventional Fe-Ni-Cr-Mo-Cu alloy.
The solution of patent document 1 improves the corrosion resistance of the alloy, but does not improve the melt cuttability.
Documents of the prior art
Patent document
Patent document 1: JP2018-172709A publication
Disclosure of Invention
Problems to be solved by the invention
In view of the above circumstances, an object of the present invention is to provide an Fe-Ni-Cr-Mo-Cu alloy that can prevent the occurrence of cracks even if cut by melt-cutting, and also can prevent the occurrence of melting loss and attachment of dross at the upper edge portion.
Means for solving the problems
The inventors have made intensive studies to solve the above problems. First, as a preliminary test, an alloy of 30 mass% Ni-25 mass% Cr-8 mass% Mo-4 mass% Cu-0.25 mass% N with the balance being Fe was prepared by an electric furnace, heat-treated in a heat treatment furnace at 1150 ℃ for a soaking time of 8 hours, and then hot-rolled to a thickness of 20mm to obtain an alloy sheet. Then, the surface was subjected to shot blasting to remove scale, and the sample was cut into 100mm × 300mm pieces and plasma-cut (fusion-cut).
For the melt-cutting, an ECONOGRAPH-4000 plasma cutter (available from SCHOTOKIN CO., LTD.) was used, and argon gas was used as a plasma gas. The cutting conditions were set as follows: current 300A, cutting speed 500 mm/min, 1000 mm/min, 1500 mm/min, gas flow 20L/min. As evaluation items of the melt-cuttability of the test material, the presence or absence of cracks and the degree of melting loss (dent) of the upper edge portion after melt-cutting were measured by digital microscope observation. In addition, regarding the adhesion of the dross to the test material, the test material in which the adhesion of the dross was not confirmed by the digital microscope was judged as "o", the test material in which the dross was removed by air hammer grinding as machining was judged as "Δ", and the test material in which the dross was difficult to be removed by the air hammer grinding as machining and the dross was required to be removed by sawing was judged as "x". The "upper edge portion" refers to an edge portion on the side irradiated with plasma.
The appropriate cutting speed varied depending on the thickness of the test piece, and as a result of the preliminary test, when the cutting speed was slow, 500 mm/min, the melt cutting was possible, but the cutting speed was slow, so that heat was difficult to remove, and melt loss (dent) occurred in the upper edge portion after the melt cutting. On the other hand, when the cutting speed was 1500 mm/min, a partially non-penetrated portion was generated, and the fusion cutting was not performed. On the other hand, as shown in fig. 1, when the cutting speed was 1000 mm/min, the cutting speed was 1000 mm/min as a test condition, because it was possible to prevent the occurrence of melting damage (dent) on the upper edge portion 12 of the melt-cut surface 11 and the adhesion of dross on the lower edge portion 13 of the melt-cut surface 11 with respect to the melt-cut surface 11 of the alloy plate 10 having the plate thickness t, and to obtain a good cut surface. Further, focusing on the components of Si, Al, Ti, Sn, and Zn, which are trace elements in each alloy, it was found that good melt cuttability can be obtained within a certain range of a certain amount. FIG. 1 is an explanatory view showing the state of the melt-sliced surface of the Fe-Ni-Cr-Mo-Cu alloy of the present invention.
It has also been found that excellent hot-cutting properties can be imparted by controlling the Cu concentration added to improve the corrosion resistance of the alloy within a certain range. On the other hand, it was found that if the amount of Cu added is more than a predetermined amount, a shear crack occurs. It is considered that the reason why the addition of Cu causes the occurrence of the shear cracks is that Cu is concentrated in the final solidification portion of the slab, and it was found that the occurrence of the shear cracks is suppressed when the concentration of Cu in the final solidification portion is reduced by changing the heat treatment conditions before hot rolling.
The gist of the configuration of the present invention is as follows.
[1] An Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion, which comprises:
carbon (C): 0.004 to 0.025 mass%,
Silicon (Si): 0.02 to 0.60 mass%,
Manganese (Mn): 0.03 to 0.35 mass%,
Phosphorus (P): 0.040 mass% or less,
Sulfur (S): 0.003 mass% or less,
Nickel (Ni): 30.0 to 40.0 mass%,
Chromium (Cr): 21.0 to 25.0 mass%,
Molybdenum (Mo): 6.50 to 8.00 mass percent,
Nitrogen (N): 0.18 to 0.28 mass%,
Copper (Cu): 2.50 to 5.00 mass%,
Aluminum (Al): 0.001 to 0.100 mass%,
Titanium (Ti): 0.001 to 0.010 mass%,
Tin (Sn): 0.001 to 0.050% by mass, and
zinc (Zn): 0.001 to 0.030 mass%,
the balance being iron (Fe) and unavoidable impurities.
[2] The Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion according to [1], which satisfies the following formula (1) (in the formula (1), the symbol of each element represents the content (% by mass) of the element).
-10≤80Al+700Ti+300Sn+400Zn-30Si≤35···(1)
[3] The Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion according to [1] or [2], which satisfies the following formula (2) (in the formula (2), the symbol of each element represents the content (% by mass) of the element).
Cu≤-0.1×(80Al+700Ti+300Sn+400Zn-30Si)+8···(2)
[4] The Fe-Ni-Cr-Mo-Cu alloy for hot-cutting as set forth in any one of [1] to [3], wherein a Cu concentration d on a mass basis at a portion between tx (1/2) and tx (1/3) at a central portion of a plate thickness t (unit: mm) of the Fe-Ni-Cr-Mo-Cu alloy satisfies the following expression (3) (in the expression (3), [ Cu concentration% ] represents a% Cu concentration on a mass basis of the entire Fe-Ni-Cr-Mo-Cu alloy).
0.80 × [ Cu concentration% ]. ltoreq.Cu concentration d ≦ 1.20 × [ Cu concentration% ]. cndot. (3)
ADVANTAGEOUS EFFECTS OF INVENTION
According to the Fe-Ni-Cr-Mo-Cu alloy of the present invention, even if cutting is performed by melt cutting, generation of cracks can be prevented, and occurrence of melting loss and attachment of dross at the upper edge can also be prevented.
Drawings
FIG. 1 is an explanatory view showing the state of the melt-sliced surface of the Fe-Ni-Cr-Mo-Cu alloy of the present invention.
FIG. 2 is a graph showing the relationship between the value of the formula (1) and the value of the formula (2) in the composition of the Fe-Ni-Cr-Mo-Cu alloy and the shear properties with respect to the Cu content.
FIG. 3 is an explanatory view showing a melt-sliced state of a conventional Fe-Ni-Cr-Mo-Cu alloy.
Detailed Description
Next, the details of the Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion of the present invention will be described. The Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion contains carbon (C): 0.004 to 0.025 mass%, silicon (Si): 0.02 to 0.60 mass%, manganese (Mn): 0.03 to 0.35 mass%, phosphorus (P): 0.040 mass% or less, sulfur (S): 0.003 mass% or less of nickel (Ni): 30.0 to 40.0 mass%, chromium (Cr): 21.0 to 25.0 mass%, molybdenum (Mo): 6.50 to 8.00 mass%, nitrogen (N): 0.18-0.28 mass%, copper (Cu): 2.50 to 5.00 mass%, aluminum (Al): 0.001 to 0.100 mass%, titanium (Ti): 0.001 to 0.010 mass%, tin (Sn): 0.001 to 0.050% by mass and zinc (Zn): 0.001 to 0.030 mass%, the balance being iron (Fe) and unavoidable impurities.
Carbon (C): 0.004 to 0.025 mass%
C in Fe-Ni-Cr-Mo-Cu alloys for use in hot-cutting is an element that affects the strength of the alloys, and if the content of C is small, sufficient strength required as a structural material cannot be obtained. Therefore, the lower limit of the content of C is set to 0.004 mass%. On the other hand, if the content of C is large, carbide such as Cr is formed, and the corrosion resistance is lowered. Therefore, the upper limit of the content of C is set to 0.025 mass%. The lower limit of the content is preferably 0.005 mass%, and the lower limit of the content is particularly preferably 0.006 mass%. Further, the upper limit of the content is preferably 0.023 mass%, and the upper limit of the content is particularly preferably 0.021 mass%.
Silicon (Si): 0.02 to 0.60% by mass
Si in the Fe-Ni-Cr-Mo-Cu alloy for cutting is added as a deoxidizer. In addition, Si has an effect of improving the fluidity of molten steel, that is, reducing the viscosity of molten steel, and is an element that significantly improves the melt-cuttability. Therefore, the lower limit of the content of Si is set to 0.02 mass%. On the other hand, if the Si content is large, the precipitation of the σ phase is promoted, and therefore, the corrosion resistance is deteriorated. Therefore, the upper limit of the content of Si is set to 0.60 mass%. The lower limit of the content is preferably 0.05 mass%, and the lower limit of the content is particularly preferably 0.10 mass%. The upper limit of the content is preferably 0.50 mass%, and the upper limit of the content is particularly preferably 0.25 mass%.
Manganese (Mn): 0.03 to 0.35% by mass
Mn in the Fe-Ni-Cr-Mo-Cu alloy for cutting is added as an element having a deoxidizing effect. In addition, Mn has an effect of improving the fluidity of molten steel. Therefore, the lower limit of the Mn content is set to 0.03 mass%. On the other hand, a large Mn content deteriorates the corrosion resistance. Therefore, the upper limit of the content of Mn is set to 0.35 mass%. The upper limit of the content is preferably 0.30 mass%, and the upper limit of the content is particularly preferably 0.25 mass%.
Phosphorus (P): 0.040 mass% or less
When the content of P in the Fe-Ni-Cr-Mo-Cu alloy for hot-cutting is large, P segregates at grain boundaries, and the hot workability and corrosion resistance deteriorate. Therefore, the upper limit thereof needs to be strictly defined. In the present invention, P is limited to 0.040 mass% or less. The upper limit of the content is preferably 0.030 mass%, and the upper limit of the content is particularly preferably 0.020 mass%. The lower limit of the content of P is preferably as close to 0%, and examples thereof include 0.001% by mass.
Sulfur (S): 0.003 mass% or less
In the Fe-Ni-Cr-Mo-Cu alloy for hot-cutting, if the S content is large, it segregates at grain boundaries, and the hot workability is deteriorated. Therefore, the upper limit thereof needs to be strictly defined. In the present invention, S is limited to 0.003 mass% or less. The upper limit of the content is preferably 0.002 mass%, and the upper limit of the content is particularly preferably 0.001 mass% or less. The lower limit of the content of S is preferably as close to 0%, and examples thereof include 0.0001%.
Nickel (Ni): 30.0 to 40.0% by mass
Ni in the Fe-Ni-Cr-Mo-Cu alloy for cutting is an element which suppresses precipitation of intermetallic compounds such as sigma phase and improves corrosion resistance such as general corrosion resistance. Therefore, the lower limit of the Ni content is set to 30.0 mass%. On the other hand, when the Ni content is large, the thermal deformation resistance increases, the hot workability decreases, and the cost increases. Therefore, the upper limit of the Ni content is set to 40.0 mass%. The lower limit of the content is preferably 32.0 mass%, and the lower limit of the content is particularly preferably 34.0 mass%. The upper limit of the content is preferably 39.5 mass%, and the upper limit of the content is particularly preferably 39.0 mass%.
Chromium (Cr): 21.0 to 25.0% by mass
Cr in the Fe-Ni-Cr-Mo-Cu alloy for cutting is an element for comprehensively improving corrosion resistance such as pitting corrosion resistance, crevice corrosion resistance, general corrosion resistance and the like. Therefore, the lower limit of the content of Cr is set to 21.0 mass%. On the other hand, if the content of Cr is large, intermetallic compounds such as σ phase are likely to precipitate, resulting in a decrease in corrosion resistance. Therefore, the upper limit of the Cr content is set to 25.0 mass%. The lower limit of the content is preferably 22.0 mass%, and the lower limit of the content is particularly preferably 23.0 mass%.
Molybdenum (Mo): 6.50 to 8.00 mass%
Mo in the Fe-Ni-Cr-Mo-Cu alloy for melt cutting is an element for improving the pitting corrosion resistance and the general corrosion resistance. Therefore, the lower limit of the content of Mo is set to 6.50 mass%. On the other hand, if the content of Mo is large, intermetallic compounds such as σ are likely to precipitate, resulting in a decrease in corrosion resistance. Therefore, the upper limit of the content of Mo is set to 8.00 mass%. The lower limit of the content is preferably 6.80% by mass, and the lower limit of the content is particularly preferably 7.00% by mass.
Nitrogen (N): 0.18 to 0.28 mass%
N in the Fe-Ni-Cr-Mo-Cu alloy for fusion cutting is an element for improving the pitting corrosion resistance. Therefore, the lower limit of the content of N is set to 0.18 mass%. On the other hand, if the content of N is large, hot workability is deteriorated. Therefore, the upper limit of the content of N is set to 0.28 mass%. The lower limit of the content is preferably 0.19 mass%, and the lower limit of the content is particularly preferably 0.20 mass%. The upper limit of the content is preferably 0.27 mass%, and the upper limit of the content is particularly preferably 0.26 mass%.
Copper (Cu): 2.50 to 5.00 mass%
Cu in the Fe-Ni-Cr-Mo-Cu alloy for cutting is an element that significantly improves acid resistance and improves cutting properties by lowering the melting point of the alloy. Therefore, the lower limit of the Cu content is set to 2.50 mass%. On the other hand, when the Cu content is increased, the hot workability is deteriorated. Therefore, the upper limit of the Cu content is set to 5.00 mass%. The lower limit of the content is preferably 2.80% by mass, the more preferable lower limit of the content is 3.05% by mass, and the particularly preferable lower limit of the content is 3.15% by mass. The upper limit of the content is preferably 4.80% by mass, and the upper limit of the content is particularly preferably 4.60% by mass.
Aluminum (Al): 0.001 to 0.100 mass%
Al in the Fe-Ni-Cr-Mo-Cu alloy for the melt-cutting is an element added as a deoxidizer. When the content of Al is small, the oxygen concentration in the molten metal during the cutting increases, the viscosity also increases, and the surface of the material tends to be dented. Therefore, the lower limit of the content of Al is set to 0.001 mass%. On the other hand, if the content of Al is large, the amount of dross after melt cutting increases, and mechanical grinding and sawing are required, thereby lowering productivity. Therefore, the upper limit of the content of Al is set to 0.100 mass%. The upper limit of the content is preferably 0.070 mass%, and the upper limit of the content is particularly preferably 0.040 mass%.
Titanium (Ti): 0.001 to 0.010 mass%
Ti in the Fe-Ni-Cr-Mo-Cu alloy for cutting is added as a deoxidizer in the same manner as Al. When the content of Ti is small, the oxygen concentration in the molten metal during the melt cutting increases, the viscosity also increases, and depressions are likely to occur on the material surface. Therefore, the lower limit of the content of Ti is set to 0.001 mass%. On the other hand, when the content of Ti is large, precipitates such as Ti-N are easily formed, and surface flaws after rolling are easily caused. Therefore, the upper limit of the content of Ti is set to 0.010 mass%. The upper limit of the content is preferably 0.009 mass%, and the upper limit of the content is particularly preferably 0.008 mass%.
Tin (Sn): 0.001 to 0.050% by mass
Sn in the Fe-Ni-Cr-Mo-Cu alloy for cutting improves corrosion resistance, and the cutting property is improved by reducing the melting point of the alloy. Therefore, the lower limit of the content of Sn is set to 0.001 mass%. On the other hand, a large Sn content lowers hot workability, and a large amount of dross after melt cutting requires mechanical grinding and sawing, resulting in a low productivity. Therefore, the upper limit of the content of Sn is set to 0.050 mass%. The lower limit of the content is preferably 0.005 mass%, and the lower limit of the content is particularly preferably 0.010 mass%. The upper limit of the content is preferably 0.047% by mass, and the upper limit of the content is particularly preferably 0.044% by mass.
Zinc (Zn): 0.001 to 0.030 mass%
Zn in the Fe-Ni-Cr-Mo-Cu alloy for cutting is an element for improving the cutting property by lowering the melting point of the alloy. Therefore, the lower limit of the Zn content is set to 0.001 mass%. On the other hand, a large Zn content lowers hot workability, and a large amount of dross after melt cutting requires mechanical grinding and sawing, resulting in a low productivity. Therefore, the upper limit of the Zn content is set to 0.030 mass%. The lower limit of the content is preferably 0.005 mass%, and the lower limit of the content is particularly preferably 0.010 mass%. Further, a preferable upper limit of the content is 0.027% by mass, and a particularly preferable upper limit of the content is 0.024% by mass.
In the Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion of the present invention, boron (B), vanadium (V) and/or niobium (Nb) may be added as required.
B in the Fe-Ni-Cr-Mo-Cu alloy for cutting is an element added for improving hot workability. Therefore, the lower limit of the content of B is preferably 0.0001 mass%. On the other hand, when the content of B is large, the hot workability is rather deteriorated. Therefore, the upper limit of the content of B is preferably 0.0030 mass%, more preferably 0.0025 mass%, particularly preferably 0.0020 mass%.
V in the Fe-Ni-Cr-Mo-Cu alloy for melt cutting is an element for improving toughness. Therefore, the lower limit of the content of V is preferably 0.01 mass%. On the other hand, when the content of V is large, the processability is deteriorated. Therefore, the upper limit of the content of V is preferably 0.10 mass%, more preferably 0.09 mass%, and particularly preferably 0.08 mass%.
Nb in the Fe-Ni-Cr-Mo-Cu alloy for cutting is an element for improving pitting corrosion resistance. Therefore, the lower limit of the content of Nb is preferably 0.001 mass%. On the other hand, a large amount of Nb generates Nb carbides, which results in surface flaws after hot rolling. Therefore, the upper limit of the content of Nb is preferably 0.030 mass%, more preferably 0.028 mass%, and particularly preferably 0.025 mass%.
In the Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion of the present invention, the balance other than the above components is iron (Fe) and inevitable impurities. The Fe-Ni-Cr-Mo-Cu alloy for cutting by melting contains Fe as a main component.
When the Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion of the present invention is an alloy satisfying the above-described composition, the composition is not particularly limited, and preferably satisfies the relationship of the following formula (1).
-10≤80Al+700Ti+300Sn+400Zn-30Si≤35···(1)
In the formula (1), the symbol of each element represents the content (mass%) of the element. The Fe-Ni-Cr-Mo-Cu alloy for hot-cutting according to the present invention satisfies the relationship of the formula (1), and can exhibit more excellent hot-cutting properties, thereby obtaining an excellent hot-cut surface.
The formula (1) is obtained from the results of examples of the present application described later. That is, fig. 2 shows the relationship between the value of the formula (1) in the composition of Fe — Ni — Cr — Mo — Cu alloy and the shear properties with respect to the Cu content (in the range of 2.50 to 5.00 mass%), and it is understood from this figure that more excellent shear properties can be exhibited by satisfying the relationship of the formula (1). Further, from the results of quantitative evaluation of the state of the melting loss (dent) and dross at the upper edge of the melting surface, it is understood that "80 Al +700Ti +300Sn +400Zn-30 Si" in FIG. 2 can be used as an evaluation index by expressing the influence of each element as a coefficient.
By setting the value of 80Al +700Ti +300Sn +400Zn-30Si to 35 or less, the amount of dross after melt cutting can be reliably reduced, and mechanical grinding and sawing can be omitted, with the result that a decrease in productivity can be prevented. From the viewpoint of more reliably reducing the amount of dross after the melt-cutting, the upper limit of the value of 80Al +700Ti +300Sn +400Zn-30Si is more preferably 30, and particularly preferably 25. On the other hand, the value of 80Al +700Ti +300Sn +400Zn-30Si is set to-10 or more, whereby the viscosity of the molten metal is reliably prevented from increasing, and therefore, the occurrence of dents on the surface of the material can be reliably prevented. Since the generation of the dent can be reliably prevented, mechanical grinding and sawing can be omitted, and as a result, the reduction of productivity can be prevented. From the viewpoint of more reliably preventing the occurrence of dishing, the lower limit of the value of 80Al +700Ti +300Sn +400Zn-30Si is more preferably-5, and particularly preferably 0.
When the Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion of the present invention is an alloy satisfying the above-described composition, the composition is not particularly limited, and preferably satisfies the relationship of the following formula (2).
Cu≤-0.1×(80Al+700Ti+300Sn+400Zn-30Si)+8···(2)
In the formula (2), the symbol of each element represents the content (mass%) of the element. The Fe-Ni-Cr-Mo-Cu alloy for hot-cutting according to the present invention satisfies the relationship of the formula (2), and can exhibit more excellent hot-cutting properties and obtain an excellent hot-cut surface.
The formula (2) is obtained from the results of examples of the present application described later. That is, as is clear from the linear portion shown by the expression (2) in fig. 2, more excellent melt-cuttability can be exhibited by satisfying the relationship of the expression (2).
When the Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion of the present invention is an alloy satisfying the above-described composition, the composition is not particularly limited, but it is preferable that the Cu concentration d in the thickness t (for example, average thickness, unit: mm) of the Fe-Ni-Cr-Mo-Cu alloy satisfies the following formula (3) in terms of the mass basis at a portion between t X (1/2) and t X (1/3) in the central portion of the thickness t.
0.80 × [ Cu concentration% ]. ltoreq.Cu concentration d ≦ 1.20 × [ Cu concentration% ]. cndot. (3)
In the formula (3), [ Cu concentration% ] represents the Cu concentration% based on the mass of the entire Fe-Ni-Cr-Mo-Cu alloy, that is, represents the Cu average concentration% based on the mass of the Fe-Ni-Cr-Mo-Cu alloy. By making the Cu concentration at the center portion corresponding to the plate thickness t satisfy the relationship of the formula (3), it is possible to more reliably prevent the occurrence of cracks after the melt cutting.
Cu is likely to segregate when the Fe-Ni-Cr-Mo-Cu alloy is solidified, and a Cu-concentrated layer may be formed in the center of the thickness t of the Fe-Ni-Cr-Mo-Cu alloy. The melting point of the Cu-concentrated layer is relatively low, and therefore cracks are sometimes generated at the Cu-concentrated layer at the time of melt cutting.
By performing heat treatment at a heating temperature of 1150 to 1250 ℃ and a soaking time of 8 to 12 hours before hot rolling the Fe-Ni-Cr-Mo-Cu alloy, Cu enrichment in the central portion of the sheet thickness t is reduced to a range satisfying the relationship represented by the formula (3), and cracks after fusion cutting can be more reliably prevented. That is, by performing the heat treatment, Cu in the Fe-Ni-Cr-Mo-Cu alloy is diffused, and Cu can be prevented from being concentrated in the center of the plate thickness t. If the heating before hot rolling is less than 1150 ℃, the diffusion of Cu becomes insufficient. On the other hand, if the heating before hot rolling exceeds 1250 ℃, melting may occur at the Cu-enriched portion. If the soaking time is less than 8 hours, the diffusion of Cu becomes insufficient. On the other hand, if the soaking time exceeds 12 hours, thick scale is formed on the surface of the Fe-Ni-Cr-Mo-Cu alloy, and the surface may be damaged after rolling. The lower limit of the Cu concentration in the central portion of the sheet thickness t is more preferably 0.85 × [ Cu concentration% ], and particularly preferably 0.90 × [ Cu concentration% ]. On the other hand, the upper limit of the Cu concentration in the central portion of the plate thickness t is more preferably 1.15 × [ Cu concentration% ], and particularly preferably 1.10 × [ Cu concentration% ]. The center of the plate thickness t is t × (1/2), and the center of the plate thickness t is symmetric with respect to the center of the plate thickness t, and therefore the center of the plate thickness t is both between the center of the plate thickness t (i.e., t × (1/2)) and t × (1/3) in the upper direction and between the center of the plate thickness t (i.e., t × (1/2)) and t × (1/3) in the lower direction. As described above, the central portion of the plate thickness t is a portion having a thickness from t × (1/3) in the upper direction to t × (1/3) in the lower direction.
According to the Fe-Ni-Cr-Mo-Cu alloy of the present invention, even if cutting is performed by melt-cutting, generation of cracks can be prevented, and in addition, upper edge melting loss and dross adhesion can be prevented as shown in fig. 1. Therefore, even when the alloy sheet is subjected to the hot-cutting as a cutting means for the Fe-Ni-Cr-Mo-Cu alloy sheet, the alloy sheet can have excellent hot-cut surfaces, and therefore, the alloy sheet is excellent in workability and productivity. In addition, the Fe-Ni-Cr-Mo-Cu alloy of the present invention has excellent hot-cuttability regardless of the sheet thickness.
Therefore, the Fe — Ni — Cr — Mo — Cu alloy of the present invention has excellent corrosion resistance, and the alloy sheet is excellent in workability and production efficiency, and therefore can be suitably used as a material for, for example, a seawater environment, a chemical plant, a flue gas desulfurization device mounted on a ship, or the like.
Examples
Examples of the present invention will be described below, but the present invention is not limited to these examples as long as the gist of the present invention is not exceeded.
Examples 1 to 15 and comparative examples 1 to 9
The thickness of the cuttable Fe-Ni-Cr-Mo-Cu alloy varies depending on the output characteristics of the apparatus for melt-cutting the Fe-Ni-Cr-Mo-Cu alloy. Here, the cutting conditions are set as current: 300A, cutting speed: 1000 mm/min, gas flow: the thickness was 20mm at 20L/min, and the evaluation was performed.
Then, the raw material (i.e., an alloy based on 30Ni-25Cr-8Mo-4Cu-0.2N with Fe as the balance (base) and having various concentrations of alloying elements of Si, Al, Ti, Sn and Zn changed) was refined by an Argon Oxygen Decarburization (AOD) method or a Vacuum Oxygen Decarburization (VOD) method using a 60-ton electric furnace, and an alloy ingot was produced by continuous casting or conventional casting. Since Zn is an element that is very easily oxidized, it is added at a later stage of refining. Then, the prepared alloy ingot was heat-treated in a heat treatment furnace under heating conditions of heating temperature and heating time shown in tables 1 and 3 below, and hot rolled or hot forged to obtain an alloy sheet having a thickness of 20 mm. Then, a 200mm × 300mm sheet was cut out from the alloy sheet, and after removing surface scale by shot blasting, the alloy sheet was used as a test material (test sample) for a fusion-cutting test. During melt cutting, an ECONOGRAPH-4000 plasma cutting machine made of microcystin is used, and argon is used as plasma gas. The cutting conditions were set as current: 300A, cutting speed: 1000 mm/min, gas flow: 20L/min. The contents of the respective components in tables 1 and 3 represent mass%.
Evaluation of
(1) Crack prevention after melt cutting
The test sample after melt cutting was observed at 20-fold magnification under a digital microscope VHX-2000 (manufactured by KEYENCE), and evaluated as follows.
O: cracks after melt cutting were not confirmed by a digital microscope.
X: cracks after the melt cutting were confirmed by a digital microscope.
(2) Prevention of melting loss of upper edge portion after melt cutting
The test specimen after melt cutting was observed at 20-fold magnification under a digital microscope VHX-2000 (manufactured by KEYENCE), and the distance of the portion of the upper edge where the dent was formed was measured with the upper edge of the test specimen after melt cutting set to the zero point, and evaluated as follows.
O: the distance is less than 1 mm.
And (delta): the distance is more than 1mm and less than 4 mm.
X: the distance is more than 4 mm.
The reason why the distance of 4mm or more is represented as x is that the depressions need to be removed by grinding or sawing by mechanical polishing, which lowers productivity.
(3) Prevention of adhesion of dross
The test specimen after melt cutting was observed at 20-fold magnification under a digital microscope VHX-2000 (manufactured by KEYENCE), and evaluated as follows.
O: dross adhesion was not confirmed using a digital microscope.
And (delta): although some adhesion of the dross was confirmed by a digital microscope, the dross could be removed by grinding with a pneumatic hammer.
X: adhesion of much of the dross was confirmed by a digital microscope, and the dross was difficult to remove by air-hammer grinding and required sawing for removal.
(4) Mass-based Cu concentration distribution (Cu segregation) of test sample section
After cutting out an analysis test piece from the end of the test sample subjected to the above-described melt-shear test, a section of the alloy along the rolling direction was subjected to mirror surface polishing, and a line analysis was performed in the plate thickness direction by an electron probe microanalyzer JXA-8200 (JEOL), and the mass-based Cu concentration in the central portion (1/2) t to (1/3) t corresponding to the plate thickness and the mass-based average Cu concentration in the entire plate thickness direction were measured and evaluated as described below.
O: the Cu segregation is 0.90 to 1.10 of the average concentration of Cu.
And (delta): the Cu segregation is 0.80 or more and less than 0.90, or more than 1.10 and 1.20 or less of the average concentration of Cu.
X: cu segregation is less than 0.80 or more than 1.20 of the average concentration of Cu.
The contents of the elements and the evaluation results of the test samples of examples are shown in table 1 below, the production steps of the test samples of examples are shown in table 2 below, the contents of the elements and the evaluation results of the test samples of comparative examples are shown in table 3 below, and the production steps of the test samples of comparative examples are shown in table 4 below. When the 4 items of the crack prevention property after the fusion cutting, the fusion damage prevention property of the upper edge portion after the fusion cutting, the slag adhesion prevention property, and the Cu segregation were all evaluated as ∘, the overall evaluation was very excellent, when the 4 items included the o evaluation and the Δ evaluation, the overall evaluation was ao, when only one of the 4 items included the x evaluation, the overall evaluation was x, the one with the overall evaluation of o or more was judged as good, and the one with the overall evaluation of x was judged as bad. In tables 1 and 3 below, underlined values indicate that the numerical values are out of the range of the present invention with respect to the contents of the respective elements, underlined values indicate that the numerical values do not satisfy the relationship of formula 1 with respect to the value of formula 1, and underlined values indicate that the numerical values do not satisfy the relationship of formula 2 with respect to the value of formula 2.
[ Table 1]
[ Table 2]
| | Manufacturing process | |
| 1 | AOD → continuous casting → Hot pressing | |
| 2 | AOD → continuous casting → Hot pressing | |
| 3 | VOD → conventional casting → hot forging | |
| 4 | VOD → continuous casting → hot pressing | |
| 5 | AOD → continuous casting → Hot pressing | |
| 6 | VOD → conventional casting → hot forging | |
| 7 | VOD → continuous casting → hot pressing | |
| 8 | VOD → continuous casting → hot pressing | |
| 9 | AOD → conventional casting → hot forging | |
| 10 | AOD → conventional casting → hot forging | |
| 11 | AOD → conventional casting → hot forging | |
| 12 | AOD → conventional casting → hot forging | |
| 13 | VOD → continuous casting → hot pressing | |
| 14 | AOD → continuous casting → Hot pressing | |
| 15 | VOD → conventional casting → hot forging |
[ Table 3]
[ Table 4]
| Comparative | Manufacturing process | |
| 1 | AOD → continuous casting → Hot pressing | |
| 2 | VOD → conventional casting → hot forging | |
| 3 | AOD → conventional casting → hot forging | |
| 4 | VOD → conventional casting → hot forging | |
| 5 | VOD → continuous casting → hot pressing | |
| 6 | AOD → continuous casting → Hot pressing | |
| 7 | AOD → continuous casting → Hot pressing | |
| 8 | VOD → continuous casting → hot pressing | |
| 9 | AOD → conventional casting → hot forging |
As shown in table 1 above, the composition of the present invention is: contains carbon (C): 0.004 to 0.025 mass%, silicon (Si): 0.02 to 0.60 mass%, manganese (Mn): 0.03 to 0.35 mass%, phosphorus (P): 0.040 mass% or less, sulfur (S): 0.003 mass% or less of nickel (Ni): 30.0 to 40.0 mass%, chromium (Cr): 21.0 to 25.0 mass%, molybdenum (Mo): 6.50 to 8.00 mass%, nitrogen (N): 0.18-0.28 mass%, copper (Cu): 2.50 to 5.00 mass%, aluminum (Al): 0.001 to 0.100 mass%, titanium (Ti): 0.001 to 0.010 mass%, tin (Sn): 0.001 to 0.050% by mass and zinc (Zn): 0.001 to 0.030 mass%, and the balance being iron (Fe) and unavoidable impurities, and examples 1 to 15, wherein 4 items of the property of preventing cracking after melt cutting, the property of preventing melting loss at the upper edge portion after melt cutting, the property of preventing adhesion of dross, and Cu segregation of the Fe-Ni-Cr-Mo-Cu alloy were evaluated as Δ or more, and the alloy was evaluated as O or more in total, and had excellent melt cutting properties.
In particular, in examples 11 to 15 which also satisfied the relationship between formula 1 and formula 2 and evaluated Cu segregation as o, all of the 4 items of the crack prevention property after melt cutting, the melt-loss prevention property of the upper edge portion after melt cutting, the slag adhesion prevention property, and Cu segregation were evaluated as o, and the alloy had particularly excellent melt-cutting property. In examples 1 and 5, the composition of the present invention was contained although the upper limit of formula (1) was exceeded, and therefore, the dross adhesion prevention property was evaluated as Δ, and the dross adhesion could be prevented. In example 2, the Cu content was close to the upper limit of the composition of the present invention, and therefore the Cu segregation was evaluated as Δ, but the crack prevention property after the melt cutting was excellent, and the melt loss of the upper edge portion after the melt cutting could be prevented. In examples 3 and 6, the contents of Cu, Sn, and Zn were close to the lower limit of the composition of the present invention, and therefore, the melting loss prevention property of the upper edge portion after melt cutting was obtained, but it was evaluated as Δ. In example 4, the relationship of the formula (2) was not satisfied, and Cu segregation was evaluated as Δ, but the crack resistance after the melt cutting was excellent.
In example 7, since the Cu content is close to the upper limit of the composition of the present invention, the Cu segregation was evaluated as Δ, but the crack prevention property after the melt cutting was excellent and the melt-loss prevention property of the upper edge portion after the melt cutting was also excellent. In examples 8 and 10, the Cu content was 2.61 mass% and 3.00 mass%, respectively, and was close to the lower limit of the composition of the present invention and lower than the lower limit of the formula (1), but the composition of the present invention was contained, and the melting loss prevention property of the upper edge portion after the melt cutting was evaluated as Δ. In example 9, although the relationship between the formula (1) and the formula (2) was not satisfied, since the composition of the present invention was contained, the fusion-cut upper edge portion had the fusion-cut property and the dross adhesion resistance.
On the other hand, in comparative example 1, the content of Si and Cu exceeded the upper limit of the composition of the present invention, and therefore the anti-meltdown property of the upper edge portion after the melt cutting was not obtained. In comparative example 1, since the content of Cu exceeds the upper limit of the composition of the present invention, Cu segregation occurs, and the crack preventing property after the melt cutting is not obtained. In comparative example 1, the soaking time in the heating treatment before hot rolling was 7 hours and short, and therefore Cu segregation was not eliminated, and cracks occurred after hot cutting. In comparative example 2, the content of Si was the lower limit of detection, the flow of the molten metal during the melt cutting was poor, and the melt-loss prevention property of the upper edge portion after the melt cutting was not obtained. In comparative example 2, since the contents of Al and Sn exceed the upper limit of the composition of the present invention, a large amount of dross was adhered, and the dross adhesion preventing property was not obtained. In comparative example 3, since the content of Ti exceeds the upper limit of the composition of the present invention, Ti — N is generated, and thus surface scratches are generated. In comparative example 3, since the content of Sn exceeded the upper limit of the composition of the present invention, a large amount of dross adhered, and the dross adhesion preventing property was not obtained.
In comparative example 4, since the contents of Sn and Zn exceeded the upper limit of the composition of the present invention, a large amount of dross adhered, and the dross adhesion preventing property was not obtained. In comparative example 5, the content of Zn exceeded the upper limit of the composition of the present invention, and therefore a large amount of dross adhered, and the dross adhesion preventing property was not obtained. In comparative example 6, since the content of Ti is less than the lower limit of the composition of the present invention, the flow of the molten metal at the time of melt cutting is poor, and the melt-loss prevention property of the upper edge portion after melt cutting is not obtained. In comparative example 6, since the content of Cu exceeded the upper limit of the composition of the present invention, Cu segregation occurred, and the crack-preventing property after melt-cutting was not obtained. In comparative example 6, the soaking time in the heating treatment before hot rolling was 7 hours and short, and therefore Cu segregation was not eliminated, and cracks occurred after hot cutting.
In comparative example 7, the content of Cu exceeded the upper limit of the composition of the present invention, and therefore cracks occurred during hot rolling. In comparative example 7, since the content of Cu exceeded the upper limit of the composition of the present invention, Cu segregation occurred, and the crack-preventing property after melt-cutting was not obtained. In comparative example 7, the soaking time in the heating treatment before hot rolling was 7 hours and short, and therefore Cu segregation was not eliminated, and cracks occurred after hot cutting. In comparative example 8, since the contents of Si and Cu are less than the lower limit of the composition of the present invention, the flow of the molten metal during the melt cutting is poor, the melting point of the alloy is high, and the alloy does not melt at a high temperature, so that a remarkable dent is generated, and the melt-loss prevention property of the upper edge portion after the melt cutting is not obtained. In comparative example 9, since the contents of Al and Ti are lower than the lower limit of the composition of the present invention, the flow of the molten metal at the time of melt cutting is poor, and since the contents of Cu, Sn, and Zn are lower than the lower limit of the composition of the present invention, the melting point of the alloy becomes high, and a melt-cut uncut portion is generated.
Industrial applicability
The Fe-Ni-Cr-Mo-Cu alloy of the present invention has excellent corrosion resistance, can prevent the occurrence of cracks even when cut by melt cutting, and can prevent the upper edge from being melted and damaged and the adhesion of dross, and therefore, is excellent in workability, and can be widely used in technical fields requiring excellent corrosion resistance, such as seawater environments, chemical plants, and flue gas desulfurization devices mounted on ships.
Claims (4)
1. An Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion, comprising:
carbon (C): 0.004 to 0.025 mass%,
Silicon (Si): 0.02 to 0.60 mass%,
Manganese (Mn): 0.03 to 0.35 mass%,
Phosphorus (P): 0.040 mass% or less,
Sulfur (S): 0.003 mass% or less,
Nickel (Ni): 30.0 to 40.0 mass%,
Chromium (Cr): 21.0 to 25.0 mass%,
Molybdenum (Mo): 6.50 to 8.00 mass percent,
Nitrogen (N): 0.18 to 0.28 mass%,
Copper (Cu): 2.50 to 5.00 mass%,
Aluminum (Al): 0.001 to 0.100 mass%,
Titanium (Ti): 0.001 to 0.010 mass%,
Tin (Sn): 0.001 to 0.050% by mass, and
zinc (Zn): 0.001 to 0.030 mass%,
the balance being iron (Fe) and unavoidable impurities.
2. The Fe-Ni-Cr-Mo-Cu alloy for cutting by fusion according to claim 1, which satisfies the relationship of the following formula (1), wherein the symbol of each element in the formula (1) represents the content of the element and is represented by mass%,
-10≤80Al+700Ti+300Sn+400Zn-30Si≤35…(1)。
3. the Fe-Ni-Cr-Mo-Cu alloy for cutting by melting as set forth in claim 1 or 2, which satisfies the relationship of the following formula (2), wherein the symbol of each element in the formula (2) represents the content of the element and is represented by mass%,
Cu≤-0.1×(80Al+700Ti+300Sn+400Zn-30Si)+8…(2)。
4. the Fe-Ni-Cr-Mo-Cu alloy for hot-cutting according to any one of claims 1 to 3, wherein a thickness t of the Fe-Ni-Cr-Mo-Cu alloy satisfies a relation of the following formula (3) where a mass-based Cu concentration d at a portion corresponding to a central portion of the thickness t between tx (1/2) and tx (1/3) is represented by [ Cu concentration% ] in the formula (3) where t is mm,
0.80 × [ Cu concentration% ]. ltoreq.Cu concentration d.ltoreq.1.20 × [ Cu concentration% ] … (3).
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