CN115637389B - A995A 6A cast high-strength duplex stainless steel and manufacturing process thereof - Google Patents
A995A 6A cast high-strength duplex stainless steel and manufacturing process thereof Download PDFInfo
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Abstract
The application discloses a high-strength double-phase stainless steel cast by A995A 6A and a manufacturing process thereof, belonging to the technical field of double-phase stainless steel manufacturing. The duplex stainless steel includes: 0.01 to 0.02 percent of C, 0.6 to 0.8 percent of Si, 0.6 to 0.8 percent of Mn, less than or equal to 0.03 percent of P, less than or equal to 0.02 percent of S, 25.5 to 26.0 percent of Cr, 6.7 to 6.9 percent of Ni, 4.4 to 4.6 percent of Mo, 0.5 to 0.8 percent of Cu, 0.7 to 0.9 percent of W, 0.22 to 0.25 percent of N, 0.10 to 0.15 percent of V, 0.10 to 0.15 percent of Co, and the balance of Fe and unavoidable impurities. The components of the materials and the proper heat treatment are adjusted, so that the components in the A995A 6A cast high-strength duplex stainless steel are homogenized, grains are refined, component segregation is avoided, and the mechanical property, heat resistance and corrosion resistance are finally improved.
Description
Technical Field
The application relates to a high-strength double-phase stainless steel cast by A995A and a manufacturing process thereof, belonging to the technical field of double-phase stainless steel manufacture.
Background
A995 The duplex stainless steel of 6A, the matrix structure being ferrite + austenite. Duplex stainless steel has enhanced mechanical properties and corrosion resistance through proper composition adjustment and heat treatment. In the ASTM a995/a995M standard, ferrite levels are not specified, but these grades will form about 30% to 60% ferrite.
The product made of the material is mainly used in a corrosive gas or liquid environment, and has high requirements on mechanical properties on the premise of ensuring enough corrosion resistance. For some impeller and guide vane products used on pump equipment, higher yield strength is often required, and the existing material components and the mechanical property data of the products prepared by the heat treatment process have larger difference and cannot meet the actual requirements.
Disclosure of Invention
In order to solve the problems, the A995A cast high-strength duplex stainless steel and the manufacturing process thereof are provided, components in the A995A cast high-strength duplex stainless steel are homogenized by adjusting components of materials, grain sizes in the stainless steel are refined, component segregation is avoided, and mechanical properties, heat resistance and corrosion resistance are finally improved.
According to one aspect of the present application, there is provided an a995 a cast high strength duplex stainless steel comprising: 0.01 to 0.02 percent of C, 0.6 to 0.8 percent of Si, 0.6 to 0.8 percent of Mn, less than or equal to 0.03 percent of P, less than or equal to 0.02 percent of S, 25.5 to 26.0 percent of Cr, 6.7 to 6.9 percent of Ni, 4.4 to 4.6 percent of Mo, 0.5 to 0.8 percent of Cu, 0.7 to 0.9 percent of W, 0.22 to 0.25 percent of N, 0.10 to 0.15 percent of V, 0.10 to 0.15 percent of Co, and the balance of Fe and unavoidable impurities.
The components in the A995A cast high-strength duplex stainless steel are matched with each other, so that the mechanical strength, heat resistance and corrosion resistance of the duplex stainless steel can be improved,
proper amount of C and N elements can play the role of solid solution strengthening, improve the strength of stainless steel, but the content of C is not easy to be too high, otherwise Cr 23 C 6 、M 6 C 3 The increase in carbide content of the alloy increases the segregation tendency, which reduces the corrosion resistance, plasticity and toughness of the stainless steel. When the N content is too high, pores are easy to form during smelting and casting, and the surface quality and the comprehensive performance of the product are reduced.
Si and Mn are used as deoxidizing elements in steel, and the content of Si and Mn is increased properly, so that the impurity content can be reduced during smelting, the purity of molten steel is improved, and the comprehensive performance of stainless steel is improved. Meanwhile, the yield strength of the material can be improved by properly increasing the Si content, but too high Si content can improve the brittle transition temperature of the material and reduce the low-temperature impact property of the material. Too high Mn content promotes precipitation of hard and brittle sigma phase in the material, and also reduces toughness and low-temperature impact performance of stainless steel.
In duplex stainless steel, P and S are harmful impurity elements, and the increase of the content thereof reduces the thermoplasticity and corrosion resistance of the steel, and the production thereof should be reduced as much as possible.
Cr is the most main element of stainless steel for obtaining the stainless property, the corrosion resistance of the stainless steel can be improved by improving the content of Cr, meanwhile, the increase of the content of Cr can promote the increase of the content of ferrite, and the strength of the stainless steel can be improved. However, too high a Cr content increases the brittle transition temperature of the stainless steel and decreases the low temperature impact properties.
Ni is an austenite forming element, increasing the content of Ni can improve the austenite structure content in the duplex stainless steel, and different proportions of Ni and Cr can form different types of stainless steel and endow the duplex stainless steel with unique properties. Increasing Ni content reduces the sigma phase formation tendency in high Cr austenitic stainless steel, thereby reducing the embrittlement degree caused by sigma phase precipitation, and improving the toughness and low-temperature impact performance of the stainless steel. However, too high a Ni content promotes too high an austenite content, thereby decreasing the strength of the stainless steel.
The addition of a proper amount of Mo element can improve the corrosion resistance of the stainless steel and improve the strength and the hardness of the stainless steel. However, too high a Mo content promotes precipitation of the α' phase and the σ phase, and in particular accelerates precipitation of the χ phase, resulting in a stainless steel having reduced plasticity and toughness. As the Mo content in the stainless steel increases, the content of austenite forming elements, such as Ni, N, mn and C elements, should be correspondingly increased.
The proper amount of Cu can improve the corrosion resistance of the stainless steel, and the addition of the Cu content reduces the strength of the stainless steel, improves the toughness and improves the mechanical property, the cold processing property and the cutting processing property. However, excessive Cu is easy to generate a copper embrittlement defect, so that the hot workability of the stainless steel is deteriorated, and meanwhile, the strength of the stainless steel is reduced too much to influence the bearing capacity of a later product and the usability.
The proper amount of W can improve the corrosion resistance of stainless steel, and meanwhile, W and C form dispersed fine alloy carbide which can refine grains and improve the comprehensive performance of the stainless steel. However, when the W content is too high, hard particles tend to be generated, which affects the processability.
The stainless steel is added with trace V and Co, and the trace V and Co and C can form dispersed fine alloy carbide, so that the effect of refining grains and improving the comprehensive performance of the stainless steel is achieved. Co is expensive and hard particles are easily produced when the Co and V contents are too high to affect processability.
Optionally, cu% in the a995 a cast high strength duplex stainless steel: w%: mo%: =1: (0.95-1.35): (5.5-8.2). The Cu, the W and the Mo elements are mutually cooperated, the Cu is used for improving the corrosion resistance and the heat resistance of an austenite phase, the Mo can improve the corrosion resistance and the heat resistance of ferrite, and the proportion of the Cu to the Mo can balance the corrosion resistance and the heat resistance of ferrite and austenite, so that the corrosion resistance, the heat resistance and the mechanical strength of the whole stainless steel are improved; w plays a role in connecting austenite and ferrite phases, promotes the bonding strength of the austenite and the ferrite, and reduces microphase separation of the duplex stainless steel.
Optionally, the a995 a cast high strength duplex stainless steel comprises%mo: ni%: cr% = 1:1.50-1.55: (5.6-5.8). The arrangement of the three elements can reasonably allocate the proportion of austenite and ferrite in a metallographic structure, so that the corrosion resistance of the duplex stainless steel is optimal, and the tensile strength and the yield strength of the stainless steel are improved.
Optionally, the ferrite content in the A995A 6A cast high-strength duplex stainless steel is 47% -56%, and the rest is austenite. The content of ferrite directly influences the strength of a material, and the high strength can be obtained by the high ferrite content, but the high strength is biased to the characteristic of ferrite stainless steel when the material is too high, so that the brittleness of the material is too high, the elongation and the low-temperature impact performance can be obviously reduced after the tensile property is interrupted, and meanwhile, the requirement of 30-60% of the general ferrite content of the material standard is not met.
Optionally, the tensile strength of the A995A 6A cast high-strength duplex stainless steel is more than or equal to 800MPa, and the yield strength is more than or equal to 550MPa. The duplex stainless steel prepared by the components has higher tensile strength and yield strength, can meet the actual use requirement of products, and can maintain higher mechanical strength even if used for a long time, thereby prolonging the service life and the use safety of equipment prepared by the stainless steel. The duplex stainless steel is a casting material and is not subjected to a rolling process, so that on the basis of the performance, grains can be further refined if the duplex stainless steel is rolled again, and the strength of the stainless steel is improved.
Optionally, the elongation rate of the A995A 6A cast high-strength duplex stainless steel is more than or equal to 15 percent, and the impact energy at the temperature of minus 40 ℃ is more than or equal to 64J. The elongation percentage is more than or equal to 15 percent. The high elongation value represents that the austenite content in the metallographic structure of the material after component optimization is more, and the toughness is better. The low-temperature impact better represents that the proportion of austenite and ferrite in the metallographic phase of the material after the component optimization is proper, and meanwhile, the impurity content in the material is low and the structure is uniform.
Alternatively, the A995A 6A cast high strength duplex stainless steel has a hardness of 260-285HB, and the A995A cast high strength duplex stainless steel has a PREN value of 45-47. The hardness of the stainless steel is too high to represent poor structure after heat treatment, too many hard and brittle phases in the material are unfavorable for processing, and the hardness of the A995A cast high-strength duplex stainless steel is 260-285HB by combining the material components and the performance requirements of the cast material, so that the processing performance and the toughness of the duplex stainless steel can be balanced. The PREN value in stainless steel is 45-47, the PREN value=Cr% +3.3× (Mo% +0.5×W%) +16×N%, the PREN value is generally required to be more than or equal to 40 in industry, and the larger the PREN actual value, the better the corrosion resistance of the material.
According to another aspect of the present application, there is provided a process for manufacturing a995 a cast high strength duplex stainless steel according to any one of the above, comprising the steps of:
(1) Smelting C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and unavoidable impurities in an intermediate frequency induction furnace to obtain molten steel;
(2) And (3) cooling the die shell to room temperature after roasting, adjusting the temperature of molten steel to 1550-1650 ℃, casting into the die shell under normal pressure, cooling the cast by air to obtain a casting, and performing heat treatment on the casting to obtain the A995A cast high-strength duplex stainless steel.
The medium frequency induction furnace is selected for smelting, so that the production cost can be reduced, the production efficiency is high, and the method is suitable for mass production and processing.
Optionally, the smelting equipment is an intermediate frequency induction furnace with the frequency in the range of 150-10000 Hz. The equipment is suitable for special smelting equipment for smelting high-quality steel and alloy, and has the advantages of high smelting speed, high production efficiency, strong adaptability, flexible use, good electromagnetic stirring effect, convenient starting operation, coverage of molten steel by slag (reduction of pollution of the atmosphere to the molten steel) and the like. During production, the master batch made of 304 or 316L material is firstly added, the equipment frequency is regulated to 5000-8000Hz, at this time, the master batch is quickly melted under the action of a high-frequency induction coil, then other metal materials are added and smelted to 50-70% of the capacity, the required components are regulated, a deslagging agent is firstly added before the components are assayed, impurities and gas quickly overflow and are gathered into clusters under the action of the deslagging agent, and a metal rod is used for picking out. Finally, adding the die head and the waste parts which are the same as the required materials, and using the slag remover for multiple times after metal melting is needed to be carried out for slag forming because the impurities of the die head and the waste parts are more. After the molten steel is filled into the furnace, refining is started, fluorite is added according to the weight of 0.2-0.3% of the actual molten steel, and the fluorite is used as a refining agent, so that the method can be used for rapidly deoxidizing, desulfurizing, dephosphorizing and degassing. Raising the temperature of the molten steel to 1710-1720 ℃, keeping the equipment power at 8000-10000Hz, keeping for 5min for standing and floating slag operation, wherein the refined and residual tiny impurities in the molten steel can float up to the liquid level, then using a slag removing agent for primary slag removing operation, adding a deoxidizer into the molten steel, adding calcium silicate according to 0.2-0.3% of the actual weight of the molten steel for deoxidization, and then enabling the molten steel to be cast normally.
The preparation of the mould shell comprises the following steps: preparing a wax mould, coating 5-6 layers of mortar on the surface of the wax mould, wherein the mortar and sand used in each layer of the mould are not used, and the zirconium powder and the silica sol are generally used in the surface layer according to the proportion of 4.0-4.5:1, preparing slurry, coating zirconium sand, preparing slurry according to a ratio of 2.5-3.0:1 by using zirconium powder/coal gangue powder for two layers, coating 30-60 meshes of coal gangue sand, preparing slurry according to a ratio of 1.6-2.0:1 by using coal gangue powder and silica sol for three layers and then coating 16-30 meshes of coal gangue sand, and finally only adhering slurry to the final layer without coating coal gangue sand, so that pollution caused by mixing particles of the coal gangue sand into wax during dewaxing can be avoided. The thickness of the single side formed on the wax mould is not uniform, the thickness of the 1 st layer is 0.3-0.6mm, the thickness of the 2 nd layer is 0.5-0.8mm, and the thicknesses of the other layers are 1-1.4mm. And the drying time of each layer is more than or equal to 6 hours, and finally, the mold shell is obtained after slurry sealing and wax mold removal.
Optionally, the mould shell is roasted for 1-1.5 hours at 1100 ℃, so that the moisture and impurities in the mould shell can be removed, the stress of the mould shell is eliminated, and the mechanical strength of the mould shell is improved.
Optionally, the air cooling time is 0.5-1h, and the surface temperature of the mould shell can be quickly reduced to normal temperature after the air cooling.
When molten steel is cast, the mould shell is at normal temperature, the temperature of the molten steel is 1550-1650 ℃, the molten steel is cast into the mould shell under normal pressure, the operation aims at simulating a production mode of casting a metal mould, the mould shell at normal temperature is used for replacing the metal mould, the heat conductivity and the heat capacity of the mould shell are large, the cooling speed of the molten metal in the mould shell is high, the cast structure after cooling is compact, the cooling speed in air is high, the grain growth time is short, the coarsening of grains can be prevented, and meanwhile, the dendrite segregation degree generated in the casting process is reduced.
Optionally, the heat treatment in step (2) comprises:
and heating the casting to 1100-1150 ℃, preserving heat for 2-2.5h, and then cooling to room temperature by water to obtain the A995A cast high-strength duplex stainless steel. The primary heat treatment can heat and preserve heat at high temperature to ensure M generated in the casting cooling process 7 C 3 、M 23 C 6 The carbide, sigma, χ, alpha' and other intermetallic phases are redissolved and uniformly distributed, so that the proportion and the distribution non-uniformity of austenite and ferrite phases are improved. Meanwhile, austenite and ferrite are re-shaped and grown in the heating process, so that the casting structure is refined. Finally, the hard and brittle carbon is prevented by fast water coolingPrecipitation of the carbides and intermetallic phases yields austenitic and ferritic castings of suitable distribution and proportions.
Benefits of the present application include, but are not limited to:
1. according to the A995A cast high-strength duplex stainless steel, components in the stainless steel are homogenized by adjusting the material components and combining the heat treatment process, so that component segregation is avoided, the ferrite content is in the range of 47% -56%, and a duplex stainless steel product with good mechanical property, corrosion resistance and heat resistance is obtained.
2. According to the A995A cast high-strength duplex stainless steel, by limiting the proportion of Cu, W and Mo and the proportion of Mo, ni and Cr, the duplex stainless steel with good corrosion resistance and reasonable matching of toughness can be obtained.
3. According to the A995A cast high-strength duplex stainless steel, the tensile strength is more than or equal to 800MPa, the yield strength is more than or equal to 550MPa, and the mechanical property of the duplex stainless steel can be improved on the basis of ensuring higher corrosion resistance, so that the application range of the cast duplex stainless steel is improved.
4. According to the A995A cast high-strength duplex stainless steel, good mechanical properties can be maintained at 300 ℃, the tensile strength can still be maintained above 730MPa, the yield strength can still be maintained above 450MPa, and the elongation is above 26%, so that the heat resistance of the duplex stainless steel is good, and the duplex stainless steel can be used in a high-temperature place for a long time.
Drawings
The accompanying drawings, which are included to provide a further understanding of the application and are incorporated in and constitute a part of this application, illustrate embodiments of the application and together with the description serve to explain the application and do not constitute an undue limitation to the application. In the drawings:
FIG. 1 is a schematic view of a conventional test stick according to an embodiment of the present application;
FIG. 2 is a schematic view of a V-shaped test bar according to an embodiment of the present application;
fig. 3 is a schematic view of a square test bar according to an embodiment of the present application.
Detailed Description
The present application is described in detail below with reference to examples, but the present application is not limited to these examples.
Unless otherwise specified, all materials in the examples of the present application were purchased commercially, and three types of test bars were used in the examples below, in which the conventional test bars were drawn as shown in FIG. 1, with FIG. 1 (a) being a front view, FIG. 1 (b) being a left view, and FIG. 1 (c) being a top view, and were directly heat-treated and then directly processed into standard test bars having a diameter of 12.5mm according to A370 standard for tensile test; the graph of the V-shaped test bar is shown in fig. 2, the graph in fig. 2 (a) is a left view, the graph in fig. 2 (b) is a front view, the shape and the size of the V-shaped test bar meet the requirements of national standards in the United states, firstly, a semi-cylindrical test bar with the height of 29mm and the diameter of 12.7mm is taken from the lowest cylindrical part, and after heat treatment, the semi-cylindrical test bar is processed into a standard test bar with the diameter of 12.5mm according to the A370 standard for tensile test; the figure of the square test bar is shown in fig. 3, the front view of the square test bar is shown in fig. 3 (a), the left view of the square test bar is shown in fig. 3 (b), the shape of the square test bar is specially designed in the comparison test of the application, the square test bar is directly subjected to heat treatment and then is sampled from the center of the square test bar, and then the square test bar is processed into a standard test bar with phi 12.5mm according to A370 standard for tensile test.
Example 1
The embodiment relates to a high-strength duplex stainless steel cast by A995A and a manufacturing process thereof, wherein the components of the high-strength duplex stainless steel cast by A995A 6A comprise: 0.012% of C, 0.611% of Si, 0.797% of Mn, 0.015% of P, 0.018% of S, 25.92% of Cr, 6.89% of Ni, 4.58% of Mo, 0.793% of Cu, 0.886% of W, 0.249% of N, 0.103% of V, 0.142% of Co, and the balance of Fe and unavoidable impurities. Cu% in the above components: w%: mo% = 1:1.12:5.78, mo%: ni%: cr% = 1:1.5:5.66.
a995 The manufacturing process of the 6A cast high-strength duplex stainless steel comprises the following steps:
(1) Smelting C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and unavoidable impurities in an intermediate frequency induction furnace to obtain molten steel;
(2) Roasting a mould shell of a conventional test bar at 1100 ℃ for 2 hours, cooling to room temperature, adjusting the temperature of molten steel to 1550 ℃, casting into the mould shell under normal pressure, cooling the cast casting with air for 0.5 hour to obtain a casting, heating the casting to 1100 ℃ for primary heat treatment, wherein the heat preservation time of the primary heat treatment is 2.5 hours, and cooling to room temperature by water to obtain the A995 6A cast high-strength duplex stainless steel.
Example 2
The embodiment relates to a high-strength duplex stainless steel cast by A995A and a manufacturing process thereof, wherein the components of the high-strength duplex stainless steel cast by A995A 6A comprise: 0.017% of C, 0.765% of Si, 0.731% of Mn, 0.013% of P, 0.017% of S, 25.74% of Cr, 6.86% of Ni, 4.573% of Mo, 0.768% of Cu, 0.737% of W, 0.236% of N, 0.132% of V, 0.15% of Co, and the balance of Fe and unavoidable impurities. Cu% in the above components: w%: mo% = 1:0.96:5.95, mo%: ni%: cr% = 1:1.5:5.63.
a995 The manufacturing process of the 6A cast high-strength duplex stainless steel comprises the following steps:
(1) Smelting C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and unavoidable impurities in an intermediate frequency induction furnace to obtain molten steel;
(2) Roasting a mould shell of a conventional test bar at 1100 ℃ for 2 hours, cooling to room temperature, adjusting the temperature of molten steel to 1600 ℃, casting into the mould shell under normal pressure, cooling the cast mould shell with air for 0.5 hour to obtain a casting, heating the casting to 1130 ℃ for one heat treatment, keeping the temperature of the one heat treatment for 2 hours, and cooling the casting to room temperature by water to obtain the A995A cast high-strength duplex stainless steel.
Example 3
The embodiment relates to a high-strength duplex stainless steel cast by A995A and a manufacturing process thereof, wherein the components of the high-strength duplex stainless steel cast by A995A 6A comprise: 0.019% of C, 0.798% of Si, 0.617% of Mn, 0.012% of P, 0.013% of S, 25.51% of Cr, 6.72% of Ni, 4.43% of Mo, 0.542% of Cu, 0.716% of W, 0.223% of N, 0.105% of V, 0.112% of Co, and the balance of Fe and unavoidable impurities. Cu% in the above components: w%: mo% = 1:1.32:8.17, mo%: ni%: cr% = 1:1.52:5.76.
a995 The manufacturing process of the 6A cast high-strength duplex stainless steel comprises the following steps:
(1) Smelting C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and unavoidable impurities in an intermediate frequency induction furnace to obtain molten steel;
(2) Roasting a mould shell of a conventional test bar at 1100 ℃ for 2 hours, cooling to room temperature, adjusting the temperature of molten steel to 1650 ℃, casting into the mould shell under normal pressure, cooling the cast mould shell with air for 1 hour to obtain a casting, heating the casting to 1150 ℃, carrying out primary heat treatment, keeping the temperature of the primary heat treatment for 2 hours, and cooling the casting to room temperature by water to obtain the A995A cast high-strength duplex stainless steel.
Example 4
The difference between this example and example 2 is that in step (2) of the manufacturing process of the high-strength duplex stainless steel cast by a995 a, the V-shaped test bar in fig. 2 is cast by molten steel, and the rest of the components and the manufacturing steps are the same as those of example 2, so that the high-strength duplex stainless steel cast by a995 a is obtained.
Example 5
The difference between this example and example 2 is that in step (2) of the manufacturing process of the high-strength duplex stainless steel cast by a995 a, the square test bar in fig. 3 is cast by molten steel, and the rest of the components and the manufacturing steps are the same as those of example 2, so that the high-strength duplex stainless steel cast by a995 a is obtained.
Example 6
The difference between this example and example 2 is that in step (2) of the manufacturing process of casting high-strength duplex stainless steel by using a995 a, the manufacturing process further comprises a secondary heat treatment, and the casting after the primary heat treatment and water cooling to room temperature is heated to 650 ℃ again for the secondary heat treatment, wherein the heat preservation time of the secondary heat treatment is 1.5h, so as to obtain the high-strength duplex stainless steel cast by using a995 a.
Example 7
The difference between this example and example 2 is that in step (2) of the manufacturing process of the high-strength duplex stainless steel cast by a995 a, the manufacturing process further comprises a secondary heat treatment, the casting after the primary heat treatment and water cooling to room temperature is cooled to 700 ℃ for the secondary heat treatment, and the heat preservation time of the secondary heat treatment is 1h, so that the high-strength duplex stainless steel cast by a995 a 6A is obtained.
Example 8
This example differs from example 2 in that the composition of the a995 a cast high strength duplex stainless steel is changed, the Cu content is 0.708%, the W content is 0.81%, and at this time the Cu%: w%: mo% = 1:1.14:6.46, the proportion of the rest components and the manufacturing steps are the same as those of the example 2, and the cast high-strength duplex stainless steel A995 6A is obtained.
Example 9
The difference between this example and example 2 is that the composition of the a995 a cast high strength duplex stainless steel is changed, the Mo element content is 4.417%, ni 6.892%, at this time Mo%: ni%: cr% = 1:1.56:5.83, the proportion of the rest components and the manufacturing steps are the same as those of the example 2, and the cast high-strength duplex stainless steel A995 6A is obtained.
Example 10
The difference between this example and example 2 is that in step (2) of the manufacturing process of the high-strength duplex stainless steel cast by a995 a, the heat treatment process after casting is different, the primary heat treatment of the cast is changed to heat-preserving the cast at 1080 ℃ for 2 hours, the primary heat treatment is performed, the air is cooled to room temperature, and the rest of the components are the same as those of the manufacturing process of example 2, so that the high-strength duplex stainless steel cast by a995 a is obtained.
Example 11
The difference between this example and example 2 is that in step (2) of the manufacturing process of A995A cast high strength duplex stainless steel, the heat treatment process after casting is different, the casting is warmed up to 1130 ℃ and kept for 2 hours, then furnace cooled to 1050 ℃ and kept for 1 hour, then air cooled to room temperature, the rest of the components are the same as those of example 2, and the A995A cast high strength duplex stainless steel is obtained
Comparative example 1
The comparative example relates to a A995A 6A cast high-strength duplex stainless steel and a manufacturing process thereof, wherein the A995A cast high-strength duplex stainless steel comprises the following components: 0.032% of C, 0.733% of Si, 0.456% of Mn, 0.033% of P, 0.027% of S, 24.48% of Cr, 7.39% of Ni, 3.872% of Mo, 1.126% of Cu, 0.979% of W, 0.284% of N, 0.099% of V, 0.089% of Co, and the balance of Fe and unavoidable impurities.
The manufacturing steps of the A995A cast high-strength duplex stainless steel are the same as those of the embodiment 2, and the A995A cast high-strength duplex stainless steel is obtained.
Comparative example 2
The comparative example relates to a A995A 6A cast high-strength duplex stainless steel and a manufacturing process thereof, wherein the A995A cast high-strength duplex stainless steel comprises the following components: 0.019% of C, 0.504% of Si, 0.467% of Mn, 0.02% of P, 0.015% of S, 26.25% of Cr, 6.41% of Ni, 3.382% of Mo, 0.518% of Cu, 0.535% of W, 0.187% of N, 0.101% of V, 0.081% of Co, and the balance of Fe and unavoidable impurities.
The manufacturing steps of the A995A cast high-strength duplex stainless steel are the same as those of the embodiment 2, and the A995A cast high-strength duplex stainless steel is obtained.
Test example 1
The cast high strength duplex stainless steel of a995 a prepared in the above examples and comparative examples was directly subjected to performance test, and the results are shown in table 1 below.
In table 1, pren=cr% +3.3× (Mo% +0.5×w%) +16×n%, and the hardness of the test bar was measured using a brinell hardness tester, and the ferrite content was obtained by calculation according to the formula in the a800/a800M-01 standard and look-up table.
TABLE 1
From the data in table 1, it can be seen that:
1) As can be seen from comparison of test data of examples 1, 2 and 3, when the content of each element of the dual-phase stainless steel cast by the A995A material is between 49 and 56 percent, the tensile strength is basically above 800MPa after solution treatment at 1100-1150 ℃, the yield strength is basically above 580MPa, and the elongation is basically above 20 percent when the content of each element is between 800MPa, 0.12-0.19 percent, 0.611-7.99 percent, 0.617-0.797 percent, 25.51-25.92 percent, 6.72-6.89 percent, 4.435-4.573 percent, 0.542-0.793 percent, 0.013-0.132 percent, 0.716-0.886 percent, 0.112-0.150 percent and 0.223-0.249 percent; the low-temperature impact energy at the temperature of minus 40 ℃ is more than 67J. The comprehensive analysis shows that the strength index is slightly improved along with the improvement of the solid solution temperature, and the toughness index is slightly reduced. The comprehensive comparison example 2 has good toughness and better combination and optimal comprehensive performance.
2) As can be seen from comparison of the test data of examples 2, 4 and 5, under the conditions of identical material components and identical heat treatment process, the detection results of the conventional test bars, V-shaped test blocks and square test blocks still accord with each other, the tensile strength is basically above 800MPa, the yield strength is basically above 580MPa, the elongation is basically above 20 percent, and the low-temperature impact energy at minus 40 ℃ is slightly reduced to 64J. The comprehensive comparison analysis shows that the tensile strength and the elongation are slightly reduced and the yield strength is not greatly changed along with the increase of the size of the test bar. The low-temperature impact energy of the square test bar is the lowest, and the analysis is related to the fact that the relative heat preservation time of the square test bar is short and the tissue is even and insufficient when the size of the test bar is large.
3) As can be seen from comparison of the test data of examples 2, 6 and 7, after the primary heat treatment of high-temperature solid solution at 1130 ℃ and the secondary heat treatment of precipitation hardening at 650-700 ℃, the material strength index is obviously improved, and the plastic index is obviously reduced. Wherein the tensile strength is improved by 85MPa at the highest, the elongation is reduced by about 33% at the highest, and the low-temperature impact energy at-40 ℃ is reduced by about 60%. Therefore, although the strength can be improved through precipitation hardening treatment after solid solution, the plasticity index is reduced too much, and the method is not suitable for production application and can be only used as a reference index for measuring the material performance under the limit condition.
4) As can be seen from comparative analysis of the test data in examples 2, 8 and 9, when Ni in the material composition is increased to 6.892% and Mo is reduced to 4.417%, the elongation and low-temperature impact performance are slightly improved, but the strength is the lowest of three schemes, wherein the tensile strength is reduced to 802MPa and the yield strength is reduced to 559MPa.
5) As can be seen from comparative analysis of the test data of examples 2, 10 and 11, under the condition of the same components, the solid solution temperature is reduced to 1080 ℃, or after the solid solution is heated to 1130 ℃ at high temperature and precooled to 1050 ℃ for uniform temperature, the strength index is reduced, wherein the tensile strength is reduced to 807MPa, and the yield strength is reduced to 565MPa.
6) As can be seen from comparative analysis of the test data of example 2 and comparative examples 1 and 2, under the same conditions of the heat treatment process, the Cr content was reduced from 25.74% to 24.48%, the Ni content was increased from 6.86% to 7.39%, and the Mo content was reduced from 4.573% to 3.872%, but the material elongation and low-temperature impact were increased, but the strength index was significantly decreased, wherein the tensile strength was decreased by 67MPa and the yield strength was decreased by 106MPa.
7) As can be seen from comparative analysis of the test data of examples 1-11, the cast duplex stainless steel made of the A995A material has the hardness of 260-297HB at the tensile strength of 802-927MPa and the hardness of 260-283HB at the tensile strength of 802-847 MPa. Although there is a tendency of high strength and high hardness, there is no linear conversion relationship between strength and hardness, and analysis is related to the microscopic distribution of ferrite and austenite in cast duplex stainless steel.
Comprehensive analysis shows that in the cast duplex stainless steel composition of the A995A material, when C0.01% -0.02%, si 0.6% -0.8%, mn 0.6% -0.8%, P less than or equal to 0.03%, S less than or equal to 0.02%, cr25.5% -26.0%, ni6.7% -6.9%, mo4.4% -4.6%, cu 0.5% -0.8%, W0.7% -0.9%, N0.22% -0.25%, V0.10% -0.15% and Co 0.10% -0.15%, the theoretical calculation ferrite content is 47% -56%. After the material test bar is subjected to water-cooling solution treatment at 1100-1150 ℃ for 2-2.5h, the tensile strength is more than or equal to 800MPa, and the yield strength is more than or equal to 550MPa; the elongation rate is more than or equal to 15 percent, the impact energy at minus 40 ℃ is more than or equal to 64J, and the hardness is between 260 HB and 283 HB.
Test example 2
The a995 a cast high strength duplex stainless steel prepared in the above examples and comparative examples was processed into a 10mm diameter standard bar, then heated to 300 ℃ and incubated for 0.5h, after which high temperature performance test was performed at 300 ℃ and the results are shown in table 2 below.
The calculation formula of the tensile strength decrease rate in table 2 is: the formula for calculating the reduction rate of the yield strength and the elongation is the same as the formula for calculating the reduction rate of the yield strength and the elongation, wherein [ (tensile strength before heat preservation at 300 ℃ and tensile strength before heat preservation at 300 ℃)/tensile strength before heat preservation at 300 ℃ is multiplied by 100%.
TABLE 2
From the data in Table 2, it is found that the samples of examples 1, 2, 3, 4, 5, 8, 9, 10, and 11 had tensile strengths of 730MPa or more, yield strengths of 450MPa or more, and elongations of 26% or more after heat preservation at 300℃for 0.5 hours. The tensile strength of the samples of examples 6 and 7 after precipitation hardening treatment can still be maintained above 800MPa, but the elongation is significantly reduced, at least 19%. The tensile strength of the test pieces of comparative examples 1 and 2 was low, at a minimum of 687MPa, but the elongation was high, at a maximum of 33%. The tensile strength is generally reduced by about 10%, the yield strength is generally reduced by about 18.5%, and the elongation is increased by about 16% compared to the room temperature and high temperature properties.
Test example 3
Corrosion resistance experiments were performed on A995A cast high strength duplex stainless steel prepared in examples and comparative examples according to ASTM G48 Standard method A: the test results are shown in Table 3.
TABLE 3 Table 3
| Sample of | PREN value | Weight loss g/m 2 |
| Example 1 | 46.5 | 0.25 |
| Example 2 | 45.8 | 0.22 |
| Example 3 | 44.9 | 035 |
| Example 4 | 45.8 | 0.19 |
| Example 5 | 45.8 | 0.31 |
| Example 6 | 45.8 | 6.8 |
| Example 7 | 45.8 | 7.4 |
| Example 8 | 46.2 | 0.47 |
| Example 9 | 47.0 | 0.54 |
| Example 10 | 45.8 | 0.37 |
| Example 11 | 45.8 | 0.27 |
| Comparative example 1 | 43.4 | 1.04 |
| Comparative example 2 | 41.3 | 1.21 |
As can be seen from the data in Table 3, the samples of examples 1, 2, 3, 4, 5, 8, 9, 10 and 11 have PREN values of 45 or more, and the test results show that the weight loss is 0.54g/m or less 2 . The comparative examples have PREN values of 41.3-43.4 and the test results show a weight loss of 1.04-1.21g/m 2 And better corrosion resistance compared with the embodiment. The test results of examples 6 and 7 show that, although the PREN value is not less than 45, the weight loss after precipitation hardening treatment is greater than that of the comparative example and reaches 7.4g/m at maximum 2 The corrosion resistance of the alloy is obviously reduced after precipitation hardening treatment, and analysis is related to the fact that Cr, mo and other alloy elements which are originally dissolved in a matrix during precipitation hardening treatment are separated out to form intermetallic phases, so that local lean corrosion resistance elements are caused, and the corrosion resistance of the alloy is reduced.
The foregoing is merely exemplary of the present application, and the scope of the present application is not limited to the specific embodiments, but is defined by the claims of the present application. Various modifications and changes may be made to the present application by those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the technical ideas and principles of the present application should be included in the protection scope of the present application.
Claims (7)
1. A995 a cast high strength duplex stainless steel comprising: c (C)
0.01 to 0.02 percent, 0.6 to 0.8 percent of Si, 0.6 to 0.8 percent of Mn, less than or equal to 0.03 percent of P, less than or equal to 0.02 percent of S, 25.5 to 26.0 percent of Cr, 6.7 to 6.9 percent of Ni, 4.4 to 4.6 percent of Mo, 0.5 to 0.8 percent of Cu, 0.7 to 0.9 percent of W, 0.22 to 0.25 percent of N, 0.10 to 0.15 percent of V, 0.10 to 0.15 percent of Co, and the balance of Fe and unavoidable impurities;
cu% in the A995A cast high-strength duplex stainless steel: w%: mo% = 1: (0.95-1.35): (5.5-8.2);
mo% in the a995 a cast high strength duplex stainless steel: ni%: cr% = 1:1.50-1.55: (5.6-5.8).
2. The a995 6A cast high strength duplex stainless steel according to claim 1, wherein the a995 a cast high strength duplex stainless steel has a ferrite content of 47-56% and the balance being austenite.
3. The a995 a cast high-strength duplex stainless steel according to claim 1, wherein the a995 a cast high-strength duplex stainless steel has a tensile strength of 800MPa or more and a yield strength of 800MPa or more
550MPa。
4. The a995 6A cast high strength duplex stainless steel of claim 1, wherein the a995 a cast high strength duplex stainless steel has an elongation of 15% or more and an impact energy of 64J or more at-40 ℃.
5. The a995 6A cast high strength duplex stainless steel according to claim 1, wherein the a995 a cast high strength duplex stainless steel has a hardness of 260-285HB and the a995 a cast high strength duplex stainless steel has a PREN value of 45-47.
6. The process for manufacturing a995 a cast high strength duplex stainless steel according to any one of claims 1-5, comprising the steps of:
(1) Smelting C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and unavoidable impurities in an intermediate frequency induction furnace to obtain molten steel;
(2) And (3) cooling the die shell to room temperature after roasting, adjusting the temperature of molten steel to 1550-1650 ℃, casting into the die shell under normal pressure, cooling the cast by air to obtain a casting, and performing heat treatment on the casting to obtain the A995A cast high-strength duplex stainless steel.
7. The manufacturing process according to claim 6, wherein the heat treatment in step (2) comprises:
and heating the casting to 1100-1150 ℃, preserving heat for 2-2.5h, and then cooling to room temperature by water to obtain the A995A cast high-strength duplex stainless steel.
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