CN115637389A - A995 6A cast high-strength duplex stainless steel and manufacturing process thereof - Google Patents
A995 6A cast high-strength duplex stainless steel and manufacturing process thereof Download PDFInfo
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Abstract
The application discloses A995 6A casting high-strength duplex stainless steel and a manufacturing process thereof, belonging to the technical field of duplex 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 Mo4, 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 inevitable impurities. The method has the advantages that the components of the material are adjusted and the proper heat treatment is carried out, so that the components in the A995 6A cast high-strength duplex stainless steel are homogenized, the grains are refined, the component segregation is avoided, and the mechanical property, the heat resistance and the corrosion resistance are finally improved.
Description
Technical Field
The application relates to a A995 6A casting high strength duplex stainless steel and its manufacturing process, it is the duplex stainless steel to make the technical field.
Background
A995 In the duplex stainless steel of 6A, the matrix structure is ferrite + austenite. The duplex stainless steel has enhanced mechanical properties and corrosion resistance by appropriate 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.
Because the product made of the material is mainly used in the environment with corrosive gas or liquid, the product has higher 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 mechanical property data of the products prepared by the existing material components and heat treatment process have larger difference and cannot meet the actual requirement.
Disclosure of Invention
In order to solve the problems, the A995 6A cast high-strength duplex stainless steel and the manufacturing process thereof are provided, the components in the A995 6A cast high-strength duplex stainless steel are homogenized by adjusting the components of the material, the grain size in the stainless steel is refined, the component segregation is avoided, and the mechanical properties, heat resistance and corrosion resistance are finally improved.
According to one aspect of the present application, there is provided a995 6A 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 inevitable impurities.
The components in the A995 6A cast high-strength duplex stainless steel are mutually matched, 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 a role in solid solution strengthening to improve the strength of the stainless steel, but the C content is not easy to be too high, otherwise, cr is not easy to be too high 23 C 6 、M 6 C 3 The increase of carbide content of the isoalloy and the increase of segregation tendency can reduce the corrosion resistance, plasticity and toughness of the stainless steel. When the content of N is too high, pores are easily formed during smelting and pouring, and the surface quality and comprehensive performance of the product are reduced.
Si and Mn exist in steel as deoxidizing elements, the content of Si and Mn is increased in a proper amount, the content of impurities 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 increasing the Si content to a proper extent, but the brittle transition temperature of the material can be increased and the low-temperature impact property of the material can be reduced by increasing the Si content to an excessive extent. Too high a Mn content promotes the precipitation of hard and brittle sigma phase in the material, which also reduces the toughness and low temperature impact properties of the 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 minimized.
Cr is the most main element for stainless steel to obtain rust resistance, and increasing the Cr content can improve the corrosion resistance of the stainless steel, and meanwhile, the increase of the Cr content can promote the increase of the ferrite content and can improve the strength of the stainless steel. However, too high Cr content increases the brittle transition temperature of stainless steel and decreases the low temperature impact properties.
Ni is an austenite forming element, the content of the austenite structure in the duplex stainless steel can be improved by increasing the content of the Ni element, and different types of stainless steel can be formed by different proportions of the Ni element and the Cr element and the Ni element and the Cr element are endowed with unique properties. Increasing the Ni content reduces the tendency of sigma phase formation in high Cr austenitic stainless steels, thereby reducing the degree of embrittlement caused by the precipitation of sigma phase, and improving the toughness and low temperature impact properties of the stainless steels. However, too high Ni content contributes to too high austenite content, thereby lowering the strength of the stainless steel.
The corrosion resistance of the stainless steel can be improved by adding a proper amount of Mo element, and the strength and the hardness of the stainless steel are improved at the same time. However, too high Mo content promotes the precipitation of alpha' phase and sigma phase, especially accelerates the precipitation of chi phase, and causes the stainless steel to have lower plasticity and toughness. As the Mo content in stainless steel increases, the austenite forming elements, such as Ni, N, mn, and C element content should be increased accordingly.
The corrosion resistance of the stainless steel can be improved by a proper amount of Cu, and meanwhile, the strength of the stainless steel is reduced by adding the Cu content, the toughness is improved, and the mechanical property, the cold processing property and the cutting processing property are improved. However, excessive Cu easily generates 'copper brittleness' defect, the hot working performance of the stainless steel is deteriorated, and meanwhile, the reduction of the strength of the stainless steel is excessive, so that the bearing capacity of a product in the later period is influenced, and the use performance is influenced.
A proper amount of W can improve the corrosion resistance of the stainless steel, and simultaneously, the W and the 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 spots are likely to be generated to affect processability.
The stainless steel is added with a trace amount of V and Co which can form dispersed fine alloy carbide with C, and the effect of refining crystal grains and improving the comprehensive performance of the stainless steel is achieved. Co is expensive, and hard spots are easily generated when the contents of Co and V are too high, which affects the processability.
Alternatively, the a995 6A cast Cu% in high strength duplex stainless steel: w%: mo%: =1: (0.95-1.35): (5.5-8.2). The Cu, the W and the Mo cooperate with each other, 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 ratio of the Mo to the Mo can balance the corrosion resistance and the heat resistance of the ferrite and the 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 two phases of austenite and ferrite, promotes the bonding strength of the austenite and the ferrite, and reduces the microphase separation of the duplex stainless steel.
Alternatively, the a995 6A cast high strength duplex stainless steel has% Mo: ni%: cr% =1:1.50-1.55: (5.6-5.8). The proportion of austenite and ferrite in a metallographic structure can be reasonably adjusted by setting the three elements, so that the corrosion resistance of the duplex stainless steel can reach the best, and the tensile strength and the yield strength of the stainless steel can be improved.
Optionally, the A995 6A cast high-strength duplex stainless steel has a ferrite content of 47% -56% and the balance austenite. The content of the ferrite directly influences the strength of the material, the high ferrite content can obtain high strength, but the high ferrite content is biased to the characteristics of ferrite stainless steel when the material is too high, the brittleness of the material is too large, the elongation and the low-temperature impact performance can be obviously reduced after the tensile performance is interrupted, and the requirement of 30-60% of the general ferrite content of the material standard is not met.
Optionally, the tensile strength of the A995 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 adopting the components has higher tensile strength and yield strength, can meet the actual use requirement of products, and can still maintain higher mechanical strength after being 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 cast material and is not rolled, so that on the basis of the performance, crystal grains can be further refined if rolling is carried out, and the strength of the stainless steel is improved.
Optionally, the elongation of the A995 6A cast high-strength duplex stainless steel is more than or equal to 15%, and the impact energy at-40 ℃ is more than or equal to 64J. The elongation is more than or equal to 15 percent. The high elongation value represents that the metallographic structure of the material has more austenite content and better toughness after the composition optimization. The low-temperature impact is better, the ratio of austenite to ferrite in the gold phase of the material with optimized components is proper, the impurity content in the material is low, and the structure is uniform.
Optionally, the hardness of the A995 6A cast high strength duplex stainless steel is 260 to 285HB and the PREN value in the A995 6A cast high strength duplex stainless steel is 45 to 47. The hardness of the A995 6A cast high-strength duplex stainless steel is 260-285HB, and the processability and toughness of the duplex stainless steel can be balanced by combining the material components of the application and the performance requirements of the cast material. The PREN value in stainless steel is 45-47, the PREN value = Cr% + 3.3X (Mo% +0.5 xW%) +16 xN%, the PREN value is generally required to be more than or equal to 40 in the industry, and the higher the PREN actual value is, the better the corrosion resistance of the material is.
According to another aspect of the present application, there is provided a manufacturing process of the a995 6A cast high strength duplex stainless steel of any one of the above, including the steps of:
(1) Smelting the C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and inevitable impurities in a medium-frequency induction furnace to obtain molten steel;
(2) And roasting the mould shell, cooling to room temperature, adjusting the temperature of the molten steel to 1550-1650 ℃, casting into the mould shell at normal pressure, cooling with air after casting to obtain a casting, and carrying out heat treatment on the casting to obtain the A995 6A cast high-strength duplex stainless steel.
The production cost can be reduced by selecting the medium-frequency induction furnace for smelting, the production efficiency is high, and the method is suitable for mass production and processing.
Optionally, the smelting and using equipment is a medium-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 melting speed, high production efficiency, strong adaptability, flexible use, good electromagnetic stirring effect, convenient starting operation, covering of molten steel by furnace slag (reduction of pollution of atmosphere to molten steel) and the like. During production, firstly adding 304 or 316L master batch, adjusting the equipment frequency to 5000-8000Hz, then quickly melting the master batch under the action of a high-frequency induction coil, then adding other metal materials, melting to 50-70% of the capacity, adjusting to the required components, before testing the components, firstly adding a deslagging agent, quickly overflowing impurities and gas under the action of the deslagging agent, aggregating into clusters, and picking out by using a metal rod. And finally adding a die head and waste parts which are made of the same material as the required materials, wherein the die head and the waste parts have more impurities, so that the deslagging agent is required to be used for multiple times to remove slag after the metal is melted. After the molten steel is fully charged, refining is started, and fluorite is added according to 0.2-0.3% of the actual weight of the molten steel and is used as a refining agent, so that quick deoxidation, desulfurization, dephosphorization and degassing can be realized. Raising the temperature of the molten steel to 1710-1720 ℃, keeping the equipment power at 8000-10000Hz, keeping for 5min, standing and floating dross, floating residual micro impurities in the molten steel to the liquid level after refining, then using a deslagging agent to carry out one-time slagging operation, adding a deoxidizing agent into the molten steel, adding calcium silicon according to 0.2-0.3% of the actual weight of the molten steel for deoxidation, and then, normally casting the molten steel.
The preparation of the mould shell is as follows: preparing a wax mould, coating 5-6 layers of mortar on the surface of the wax mould, wherein the mortar and the sand used by each layer of the mould shell are not used, and the zirconium powder and the silica sol are generally used for the surface layer according to the proportion of 4.0-4.5:1 proportion configuration thick liquids, coating zircon sand, two layers use zirconium powder/coal gangue powder to dispose the thick liquids according to 2.5-3.0, coat 30-60 mesh coal gangue sand, three layers and later use coal gangue powder and silica sol to dispose the thick liquids according to 1.6-2.0, coat 16-30 mesh coal gangue sand, the last layer only glues the thick liquids, does not coat coal gangue sand, can avoid the granule of coal gangue sand to mix in the wax material and pollute when dewaxing. The thickness of the single edge formed on the wax pattern 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 thickness of the other layers is 1-1.4mm. And (3) drying each layer for more than or equal to 6 hours, and finally sealing the slurry and removing the wax mold to obtain the formwork.
Optionally, the formwork is roasted at 1100 ℃ for 1-1.5h, so that water and impurities in the formwork can be removed, the stress of the formwork is eliminated, and the mechanical strength of the formwork is improved.
Optionally, the air cooling time is 0.5-1h, and the surface temperature of the formwork can be rapidly reduced to the normal temperature through air cooling.
When the molten steel is cast, the mold shell is at normal temperature, the temperature of the molten steel is 1550-1650 ℃, the molten steel is cast into the mold shell under normal pressure, the operation aims to simulate the production mode of metal mold casting, the mold shell at normal temperature replaces a metal mold, the heat conductivity and the heat capacity of the mold shell are large, the cooling speed of the molten metal in the mold shell is high, the cooled casting is compact in structure, the cooling speed in the air is high, the grain growth time is short, the coarsening of grains can be prevented, and meanwhile, the segregation degree of dendritic crystals generated in the casting process is reduced.
Optionally, the heat treatment in step (2) comprises:
heating the casting to 1100-1150 ℃, preserving heat for 2-2.5h, and then cooling to room temperature by water to obtain A995 6A casting high strengthDuplex stainless steel. Primary heat treatment, which can make M generated in the casting cooling process through high-temperature heating and heat preservation 7 C 3 、M 23 C 6 The carbides, sigma, chi, alpha' and other intermetallic phases are re-dissolved and uniformly distributed, and the ratio and distribution nonuniformity of austenite and ferrite are improved. Meanwhile, austenite and ferrite are re-nucleated and grow up in the heating process, and the casting structure is refined. And finally, through rapid water cooling, the precipitation of hard and brittle carbides and intermetallic phases is prevented, and austenite and ferrite casting with proper distribution and proportion is obtained.
Benefits of the present application include, but are not limited to:
1. according to the A995 6A casting high strength duplex stainless steel of this application, through adjusting the material composition and heat treatment process to combine together, make the composition in the stainless steel homogenize, avoid the composition segregation, make the ferrite content in the range of 47% -56%, thus get the duplex stainless steel products with good mechanical properties, corrosion resistance and heat resistance.
2. According to the a995 6A casting high strength duplex stainless steel of the present application, by limiting the proportions of Cu, W and Mo, and the proportions of Mo, ni and Cr, it is possible to obtain duplex stainless steel having good corrosion resistance while reasonably matching toughness.
3. According to the A995 6A casting high strength duplex stainless steel of this application, its tensile strength is greater than or equal to 800MPa, the yield strength is greater than or equal to 550MPa, can guarantee to have higher corrosion resistance on the basis, improve the mechanical properties of duplex stainless steel, thus improve the application range of this casting duplex stainless steel.
4. According to the A995 6A casting high strength duplex stainless steel of this application, can still maintain better mechanical properties under 300 deg.C, its tensile strength can still be kept above 730MPa, the yield strength can still be kept above 450MPa, the elongation is above 26%, prove that this duplex stainless steel is good in heat resistance, can use for a long time under the high temperature place.
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 embodiment(s) of the application and together with the description serve to explain the application and not to limit 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 invention.
Detailed Description
The present application will be described in detail with reference to examples, but the present application is not limited to these examples.
Unless otherwise specified, the raw materials in the examples of the present application were commercially available, and three kinds of test bars were used in the following examples, wherein a conventional test bar was shown in fig. 1, fig. 1 (a) is a front view, fig. 1 (b) is a left side view, and fig. 1 (c) is a top view, and the test bar was directly heat-treated and then directly processed into a standard test bar having a diameter of 12.5mm according to a standard a370 for tensile test; the figure of the V-shaped test bar is shown in figure 2, figure 2 (a) is a left view, figure 2 (b) is a main view, the shape and the size of the V-shaped test bar meet the requirements of the national standard of America, a semi-cylindrical test bar with the height of 29mm and the diameter of R12.7mm is taken from the position of the lowest cylindrical part, 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 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 specifically designed for the comparative test of the present application, the square test bar is directly subjected to heat treatment, then is sampled from the center thereof, and is processed into a standard test bar with the diameter of 12.5mm according to the A370 standard for tensile test.
Example 1
The embodiment relates to A995 6A cast high-strength duplex stainless steel and a manufacturing process thereof, wherein the A995 6A cast high-strength duplex stainless steel comprises the following components: 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 inevitable 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 the C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and inevitable impurities in a medium-frequency induction furnace to obtain molten steel;
(2) Roasting the mould shell of the conventional test bar at 1100 ℃ for 2h, cooling to room temperature, adjusting the temperature of molten steel to 1550 ℃, casting in the mould shell under normal pressure, cooling the cast steel for 0.5h to obtain a casting, heating the casting to 1100 ℃ for primary heat treatment, wherein the heat preservation time of the primary heat treatment is 2.5h, 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 A995 6A casting high-strength duplex stainless steel and a manufacturing process thereof, wherein the A995 6A casting high-strength duplex stainless steel comprises the following components: 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 inevitable 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 the C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and inevitable impurities in a medium-frequency induction furnace to obtain molten steel;
(2) Roasting the mould shell of the conventional test bar at 1100 ℃ for 2h, cooling to room temperature, adjusting the temperature of molten steel to 1600 ℃, casting in the mould shell at normal pressure, cooling the cast steel by air for 0.5h to obtain a cast, heating the cast to 1130 ℃ for primary heat treatment, wherein the heat preservation time of the primary heat treatment is 2h, and cooling water to room temperature to obtain the A995 6A cast high-strength duplex stainless steel.
Example 3
The embodiment relates to A995 6A cast high-strength duplex stainless steel and a manufacturing process thereof, wherein the A995 6A cast high-strength duplex stainless steel comprises the following components: 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 inevitable 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 the C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and inevitable impurities in a medium-frequency induction furnace to obtain molten steel;
(2) Roasting the mould shell of the conventional test bar at 1100 ℃ for 2h, cooling to room temperature, adjusting the temperature of molten steel to 1650 ℃, casting in the mould shell under normal pressure, cooling the cast steel for 1h to obtain a casting, heating the casting to 1150 ℃ for primary heat treatment, keeping the temperature of the primary heat treatment for 2h, and cooling to room temperature by water to obtain the A995 6A cast high-strength duplex stainless steel.
Example 4
The present example is different from example 2 in that in step (2) of the manufacturing process of casting the high-strength duplex stainless steel in a995 6A, the molten steel is cast into the V-shaped test bar shown in fig. 2, and the remaining component proportions and the manufacturing steps are the same as those in example 2, so that the a995 6A cast high-strength duplex stainless steel is obtained.
Example 5
The present example is different from example 2 in that in step (2) of the manufacturing process of casting a995 6A high strength duplex stainless steel, the molten steel was cast into the square test bar shown in fig. 3, and the remaining component ratios and the manufacturing steps were the same as in example 2, to obtain a995 6A cast high strength duplex stainless steel.
Example 6
The difference between this example and example 2 is that in step (2) of the manufacturing process for casting a995 6A high-strength duplex stainless steel, the method further comprises a secondary heat treatment, wherein the casting after the primary heat treatment and water cooling to room temperature is heated again to 650 ℃ for the secondary heat treatment, and the holding time of the secondary heat treatment is 1.5h, so that the a995 6A cast high-strength duplex stainless steel is obtained.
Example 7
The difference between the embodiment and the embodiment 2 is that the step (2) of the manufacturing process for casting the high-strength duplex stainless steel by the A995 6A further comprises a secondary heat treatment, wherein 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 A995 6A cast high-strength duplex stainless steel is obtained.
Example 8
This example differs from example 2 in that the composition of a995 a cast high-strength duplex stainless steel was changed to 0.708% Cu and 0.81% W, where Cu%: w%: mo% =1:1.14:6.46, and the proportions of the other components and the manufacturing steps were the same as in example 2, to obtain A995 6A cast high-strength duplex stainless steel.
Example 9
This example is different from example 2 in that the composition of a995 6A cast high-strength duplex stainless steel was changed, the content of Mo element was 4.417%, ni 6.892%, and when Mo%: ni%: cr% =1:1.56:5.83, and the proportions of the other components and the manufacturing steps are the same as those of the example 2, thus obtaining the A995 6A cast high-strength duplex stainless steel.
Example 10
The difference between the embodiment and the embodiment 2 is that in the step (2) of the manufacturing process for casting the high-strength duplex stainless steel in the A995 6A, the heat treatment process after casting is different, the primary heat treatment of the casting is changed into the steps of heating the casting to 1080 ℃ and keeping the temperature for 2h, performing primary heat treatment, and cooling the casting to room temperature by air, and the rest components are the same as the preparation steps in the embodiment 2, so that the A995 6A cast high-strength duplex stainless steel is obtained.
Example 11
The difference between the present example and example 2 is that in step (2) of the manufacturing process of casting the high-strength duplex stainless steel in a995 a, the heat treatment process after casting is different, the casting is heated to 1130 ℃ and kept warm for 2h, then the furnace is cooled to 1050 ℃ and kept warm for 1h, then the air is cooled to room temperature, and the rest components are the same as the preparation steps in example 2, so that the a995 6A cast high-strength duplex stainless steel is obtained
Comparative example 1
The present comparative example relates to a995 a cast high-strength duplex stainless steel and a manufacturing process thereof, the composition of the a995 6A cast high-strength duplex stainless steel comprising: 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 Mo3, 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 inevitable impurities.
The procedure for producing the A995 6A cast high-strength duplex stainless steel was the same as in example 2, to obtain A995 6A cast high-strength duplex stainless steel.
Comparative example 2
The present comparative example relates to a995 a cast high-strength duplex stainless steel and a manufacturing process thereof, the composition of the a995 6A cast high-strength duplex stainless steel comprising: 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, 0.382% of Mo3, 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 inevitable impurities.
The procedure for producing the A995 6A cast high-strength duplex stainless steel was the same as in example 2, to obtain A995 6A cast high-strength duplex stainless steel.
Test example 1
The properties of the a995 6A cast high strength duplex stainless steel prepared in the above examples and comparative examples were directly measured, and the results are shown in table 1 below.
The PREN value = Cr% +3.3 × (Mo% +0.5 × W%) +16 × N% in table 1, the hardness of the test bar was measured using a brinell hardness tester, and the ferrite content was calculated according to the formula in the a800/a800M-01 standard and obtained by table lookup.
TABLE 1
From the data in table 1, it can be seen that:
1) Compared with the test data of the examples 1, 2 and 3, the A995 6A cast duplex stainless steel has the element contents of C0.12% -0.19%, si0.611% -7.99%, mn0.617% -0.797%, cr25.51% -25.92%, ni 6.72% -6.89%, mo4.435% -4.573%, cu0.542-0.793, V0.013% -0.132%, W0.716-0.886%, co0.112% -0.150% and N0.223% -0.249%, the ferrite content is 49-56%, the tensile strength is basically over 800MPa after the solution treatment at 1100-1150 ℃, the yield strength is basically over 580MPa, and the elongation is basically over 20%; the low-temperature impact work at minus 40 ℃ is more than 67J. The comprehensive analysis slightly improves the strength index along with the increase of the solid solution temperature, and slightly reduces the toughness index. The comprehensive comparative example 2 is strong and good in toughness and optimal in comprehensive performance.
2) As can be seen from comparison of the test data of the examples 2, 4 and 5, under the condition of the same material composition and the same heat treatment process, the detection results of the conventional test bar, the V-shaped test block and the square test block still accord with the rule that the tensile strength is basically more than 800MPa, the yield strength is basically more than 580MPa, the elongation is basically more than 20 percent, and the low-temperature impact power at-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 square test bar has the lowest low-temperature impact energy, and the analysis is related to the large size of the test block, short relative heat preservation time and insufficient tissue uniformity.
3) As can be seen from comparison of test data of examples 2, 6 and 7, after the same material composition is subjected to the first heat treatment of solid solution at a high temperature of 1130 ℃ and then the second heat treatment of precipitation hardening at a temperature of 650-700 ℃, the material strength index is obviously improved, and the plasticity index is obviously reduced. Wherein the tensile strength is improved by 85MPa to the maximum, the elongation is reduced by about 33% to the maximum, and the low-temperature impact energy at minus 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, so that the method is not suitable for production application and only can be used as a reference index for measuring the material performance under the limit condition.
4) As can be seen from comparative analysis of test data of examples 2, 8 and 9, when Ni in the material composition is increased to 6.892% and Mo is decreased to 4.417%, the elongation and the low-temperature impact performance are slightly improved, but the strength is the lowest of the three schemes, wherein the tensile strength is decreased to 802MPa and the yield strength is decreased to 559MPa.
5) According to comparative analysis of 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 precooling to 1050 ℃ for uniform temperature after heating at 1130 ℃ and then carrying out water cooling solid solution, the strength index has a descending trend, wherein the tensile strength is reduced to 807MPa, and the yield strength is reduced to 565MPa.
6) As can be seen from the comparative analysis of the test data of example 2 and comparative examples 1 and 2, under the same conditions of the heat treatment process, when the Cr content is reduced from 25.74% to 24.48%, the Ni content is increased from 6.86% to 7.39%, and the Mo content is reduced from 4.573% to 3.872%, the elongation and the low-temperature impact of the material are increased, but the strength index is obviously reduced, wherein the tensile strength is reduced by 67MPa, and the yield strength is reduced by 106MPa.
7) As can be seen from the comparative analysis of the test data of the examples 1 to 11, the hardness of the A995 6A casting duplex stainless steel is 260 to 297HB when the tensile strength is 802 to 927MPa, and the hardness is 260 to 283HB when the tensile strength is 802 to 847 MPa. Although the strength tends to be high and the hardness tends to be high, there is no linear conversion relationship between the strength and the hardness, and the analysis is related to the non-uniform micro-distribution of ferrite and austenite structures in the cast duplex stainless steel.
Comprehensive analysis shows that when the chemical components of the A995A cast duplex stainless steel comprise 0.01-0.02% of C, 0.6-0.8% of Si, 0.6-0.8% of Mn, less than or equal to 0.03% of P, less than or equal to 0.02% of S, 25.5-26.0% of Cr, 6.7-6.9% of Ni, 4.4-4.6% of Mo, 0.5-0.8% of Cu, 0.7-0.9% of W, 0.22-0.25% of N, 0.10-0.15% of V and 0.10-0.15% of Co, the theoretically calculated ferrite content is 47-56%. After the test bar made of the material is subjected to water-cooling solution treatment at 1100-1150 ℃ for 2-2.5h, the test tensile strength is more than or equal to 800MPa, and the yield strength is more than or equal to 550MPa; the elongation 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
A995 6A cast high-strength duplex stainless steel prepared for the above examples and comparative examples was first processed into a standard test bar with a diameter of 10mm, then heated to 300 ℃ and kept for 0.5h, and then subjected to high-temperature performance testing at 300 ℃ with the results shown in Table 2 below.
The calculation formula of the tensile strength decrease rate in table 2 is: [ (the tensile strength before the heat preservation treatment at 300 ℃ is minus the tensile strength before the heat preservation treatment at 300 ℃)/the tensile strength before the heat preservation treatment at 300 ℃) is multiplied by 100%, and similarly, the reduction rate calculation formulas of the yield strength and the elongation are also calculated according to the same calculation mode.
TABLE 2
From the data in Table 2, it is clear that the samples of examples 1, 2, 3, 4, 5, 8, 9, 10 and 11, after heat preservation at 300 ℃ for 0.5h, have tensile strengths of 730MPa or more, yield strengths of 450MPa or more and elongations of 26% or more. The tensile strength of the samples of examples 6 and 7 can still be maintained above 800MPa after the precipitation hardening treatment, but the elongation is obviously reduced to 19% at the minimum. The tensile strength of the samples of comparative examples 1 and 2 was low, 687MPa minimum, but the elongation was high, 33% maximum. Room temperature versus high temperature performance, tensile strength is generally reduced by about 10%, yield strength is generally reduced by about 18.5%, and elongation is improved by about 16%.
Test example 3
A995 6A cast high strength duplex stainless steel prepared in examples and comparative examples was subjected to corrosion resistance testing according to ASTM G48 Standard method A: the test results are shown in Table 3.
TABLE 3
| Sample (I) | 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 PREN values of the samples of examples 1, 2, 3, 4, 5, 8, 9, 10 and 11 were not less than 45, and the test results showed weight loss of not more than 0.54g/m 2 . While the PREN value of the comparative sample is between 41.3 and 43.4, the test result shows that the weight loss is between 1.04 and 1.21g/m 2 In comparison with the examples, the corrosion resistance is better. The test results of examples 6 and 7 show that, although the PREN value is 45 or more, the weight loss after precipitation hardening treatment is larger than that of the comparative example, and 7.4g/m is achieved at most 2 It is shown that the corrosion resistance is obviously reduced after the precipitation hardening treatment, and the analysis is related to that the alloy elements such as Cr, mo and the like originally dissolved in the matrix are precipitated to form intermetallic phases during the precipitation hardening treatment, so that local poor corrosion resistance elements are caused, and the corrosion resistance is reduced.
The above description is only an example of the present application, and the protection scope of the present application is not limited by these specific examples, but is defined by the claims of the present application. Various modifications and changes may occur to those skilled in the art to which the present application pertains. Any modification, equivalent replacement, improvement, etc. made within the technical idea and principle of the present application should be included in the protection scope of the present application.
Claims (9)
1. A995 a cast high strength duplex stainless steel, comprising: c
0.01 to 0.02 percent of Fe, 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 Cr25, 6.7 to 6.9 percent of Ni6, 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 inevitable impurities.
2. The a995 6A cast high strength duplex stainless steel according to claim 1, wherein said a995 6A cast high strength duplex stainless steel has a Cu% in: w%: mo% =1: (0.95-1.35): (5.5-8.2).
3. The a995 6A cast high strength duplex stainless steel according to claim 1, wherein the a995 6A cast high strength duplex stainless steel has a Mo% of: ni%: cr% =1:1.50-1.55:
(5.6-5.8)。
4. the a995 6A cast high strength duplex stainless steel according to claim 1, wherein said a995 6A cast high strength duplex stainless steel has a ferrite content of 47-56%, the remainder being austenite.
5. The A995 6A cast high-strength duplex stainless steel according to claim 1, wherein said A995 6A cast high-strength duplex stainless steel has a tensile strength of not less than 800MPa, and a yield strength of not less than 800MPa
550MPa。
6. The A995 6A cast high strength duplex stainless steel according to claim 1, wherein the elongation of said A995 6A cast high strength duplex stainless steel is equal to or more than 15%, and the ballistic work at-40 ℃ is equal to or more than 64J.
7. The a995 6A cast high strength duplex stainless steel according to claim 1, wherein the a995 6A cast high strength duplex stainless steel has a hardness of 260-285HB, and the a995 6A cast high strength duplex stainless steel has a PREN value of 45-47.
8. The process for manufacturing a995 6A cast high strength duplex stainless steel according to any one of claims 1 to 7, comprising the steps of:
(1) Smelting the C, si, mn, P, S, cr, ni, mo, cu, W, N, V, co, fe and inevitable impurities in a medium-frequency induction furnace to obtain molten steel;
(2) And roasting the die shell, cooling to room temperature, adjusting the temperature of the molten steel to 1550-1650 ℃, casting in the die shell under normal pressure, cooling with air after casting to obtain a casting, and performing heat treatment on the casting to obtain the A995 6A cast high-strength duplex stainless steel.
9. The manufacturing process according to claim 8, wherein the heat treatment in step (2) comprises:
and (3) heating the casting to 1100-1150 ℃, preserving the heat for 2-2.5h, and then cooling the casting to room temperature by water to obtain the A995 6A cast high-strength duplex stainless steel.
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