CN114717487A - 2700 MPa-grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof - Google Patents
2700 MPa-grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof Download PDFInfo
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Abstract
The invention discloses 2700MPa grade high-plasticity toughness high-corrosion resistance maraging stainless steel and a preparation method thereof, wherein the stainless steel comprises the following components: the alloy material comprises, by mass, 3.0-6.0% of Co, 7.0-9.0% of Ni, 11.0-17.0% of Cr, 0.5-2.0% of Ti, 5.0-7.0% of Mo, 0.08-1.0% of Mn, 0.08-0.5% of Si, less than or equal to 0.02% of C, less than or equal to 0.003% of P, less than or equal to 0.003% of S, and the balance of Fe. Under the conditions that C is less than or equal to 0.02 percent and Co is not more than 6 percent, the stainless steel has the tensile strength as high as 2700MPa, the elongation as high as 10 percent and the pitting potential as high as 0.24VSCE(ii) a The method can be used for key structures of long blades, ships, ocean engineering and the like for steam turbines of large thermal power units.
Description
Technical Field
The invention relates to 2700MPa grade high-ductility high-corrosion-resistance maraging stainless steel and a preparation method thereof, belonging to the field of martensitic stainless steel.
Background
The martensite precipitation strengthened stainless steel is a new steel bell developed in the 60's of the 20 th century. The corrosion-resistant steel has the strength of the maraging strengthening steel and the corrosion resistance of the stainless steel. Due to excellent comprehensive mechanical properties, the material is often used in the fields of critical high-end equipment such as aviation, aerospace, navigation and the like.
The main reason why the martensite precipitation strengthening stainless steel can realize the ultrahigh strength is that the martensite phase transformation strengthening and the aged precipitation strengthening are superposed; the main reason for the corrosion resistance is that the addition of Cr and Mo forms a passive film on the surface, thereby providing the corrosion resistance. Table 2 shows the composition and properties of commercially available high-strength stainless steels. It can be seen that the current high-strength stainless steel has the following problems: firstly, the ductility and toughness are poorer when the strength is higher; secondly, when the mechanical property is excellent, the corrosion resistance is poor; it is difficult to unify the strength, ductility and toughness and corrosion resistance to obtain excellent comprehensive performance. Therefore, how to improve the obdurability of the stainless steel on the premise of ensuring the corrosion resistance of the stainless steel so as to meet higher requirements of engineering application on the comprehensive performance of the stainless steel is a research hotspot and difficulty in the field of stainless steel, and therefore, the research on novel ultrahigh-strength maraging stainless steel with independent intellectual property rights is urgent.
Table 2 commercial high strength stainless steel compositions and properties thereof available on the market
The high content of Co ensures that the mechanical property of the high-strength stainless steel is more excellent. When the content of Co is low or 0, the comprehensive mechanical property performance is low. The Co is added into the high-strength stainless steel to form a double-edged sword, the Co can reduce the solubility of Ti and Mo in the martensite matrix, and a precipitate phase containing Mo or Ti is formed, so that the strength is improved. Meanwhile, Co can also hinder the recovery of dislocation, reduce the size of a precipitated phase and stabilize a martensite matrix, can generate higher secondary hardening, and is a guarantee for better mechanical properties such as strength and the like. Therefore, to obtain excellent mechanical properties, a large amount of Co element is inevitably added. However, the spinodal decomposition of Cr is promoted by the addition of Co to the martensitic stainless steel, and the higher the content of Co, the greater the spinodal decomposition degree of Cr, which lowers the pitting corrosion resistance of the substrate. Therefore, an appropriate amount of Co is added. The innovation of the invention is that a special structure is formed by combining optimized alloy elements, double vacuum melting and corresponding thermal mechanical treatment processes, the structure consists of martensite laths and an amorphous layer modified by lath boundaries, wherein the martensite laths contain a plurality of precipitation phases with nanometer sizes in dispersed distribution. The ultrahigh strength is obtained by the cooperative reinforcement of a plurality of nano phases; meanwhile, the amorphous decorated lath boundary promotes the dislocation multiplication and absorbs the dislocation, thereby obtaining large plasticity and huge work hardening capacity. Meanwhile, the existence of the reversed austenite also provides contribution to the plasticity and toughness of the material. On one hand, the stainless steel of the invention replaces carbon strengthening by nano-phase strengthening, so that the carbon content is greatly reduced, and on the other hand, the pitting corrosion resistance equivalent of the alloy is improved by component optimization. The extremely low carbon content and high pitting corrosion resistance equivalent design ensures excellent corrosion resistance of the stainless steel of the present invention. Therefore, compared with the existing stainless steel, the mechanical property and the corrosion resistance of the stainless steel are improved.
The invention patent application with publication number CN 102031459 a discloses a W-containing high-strength high-toughness secondary hardening stainless steel, which comprises (by mass percent) C0.10-0.20%, Cr 11.0-13.0%, Ni 2.0-3.5%, Mo 3.5-5.5%, Co 12-15%, W0.8-3.0%, V0.1-0.6%, Nb 0.01-0.06%, Si ≤ 0.2%, Mn ≤ 0.2%, S ≤ 0.01%, P ≤ 0.01%, O ≤ 30PPm, N ≤ 30PPm, and the balance Fe; the yield strength is 1300-1600 MPa, the tensile strength is 1920-2030 MPa, and the plasticity is 10-13.5%. U.S. patent 7160399 invented ultra-high strength corrosion resistant steel; the nominal composition of the alloy named as Fernium S53 is: 14.0Co, 10.0Cr, 5.5Ni, 2.0Mo, 1.0W, 0.30V, 0.21C, and the balance Fe; the room temperature ultimate tensile strength of the Fernium S53 alloy is approximately 1980MPa and the room temperature 0.2% yield stress is approximately 1560 MPa. The invention patent application with publication number CN 110358983A discloses a precipitation hardening martensitic stainless steel and a preparation method thereof, wherein the stainless steel comprises the following specific chemical components (by mass percent), 0.14-0.20% of C, 13.0-16.0% of Cr, 0.5-2.0% of Ni, 12.0-15.0% of Co, 4.5-5.5% of Mo, 0.4-0.6% of V, less than or equal to 0.1% of Si, less than or equal to 0.5% of Mn, less than or equal to 0.01% of P, less than or equal to 0.01% of S, less than or equal to 0.10% of N, and the balance of Fe; the tensile strength is 1840-1870 MPa, the yield strength is 780-820 MPa, and the elongation is 12.5-14.0%. Although the three technical schemes have the performance of high-strength stainless steel, the raw material cost is high due to the high addition of Co; the content of Co is increased, so that the scroll of Cr can be decomposed, a Cr-poor area and a Cr-rich area are further generated, and the corrosion resistance of the Cr-poor area and the Cr-rich area is reduced; the carbon content is also high, the corrosion resistance is seriously deteriorated by high carbon, the existing size, form and distribution of carbide in a matrix are difficult to control, and the mechanical property is seriously deteriorated when the size is large and appears on a grain boundary; the production process of the publication No. CN 110358983A and Ferrium S53 needs two times of aging and two times of deep cooling treatment, and the process is complex.
The patent application of the invention with the publication number of CN 107653421A discloses an ultrahigh-strength maraging stainless steel with seawater corrosion resistance, wherein the specific chemical components of the stainless steel (expressed by mass percent) are that C is less than or equal to 0.03 percent, Cr is 13.0-14.0 percent, Ni is 5.5-7.0 percent, Co is 5.5-7.5 percent, Mo is 3.0-5.0 percent, Ti is 1.9-2.5 percent, Si is less than or equal to 0.1 percent, Mn is less than or equal to 0.1 percent, P is less than or equal to 0.01 percent, S is less than or equal to 0.01 percent, and the balance is Fe. The tensile strength is 1926-2032 MPa, the yield strength is 1538-1759 MPa, the elongation is 7.5-13%, and the pitting potential Epit is more than or equal to 0.15V. Although the strengthening mechanism of the invention is a precipitation strengthening mechanism, the type of the precipitation phase is different from that of the invention, compared with the invention, the invention has no higher mechanical property and corrosion resistance, and the strengthening mechanism and the corrosion resistance of the two inventions are completely different.
The patent application publication No. CN 108251760a discloses a nanophase composite precipitation-strengthened martensitic stainless steel and a method for producing the same (in mass percent, C is 0.001 to 0.20%, Cr is 10.0 to 18.0%, Ni is 3.0 to 12.0%, Mo is 0.50 to 6.0%, Cu is 0.35 to 3.50%, Mn is 0.20 to 5.0%, Ti is 0.25 to 1.50%, Al is 0.10 to 1.0%, Si is 0.15 to 1.0%, and the balance is Fe and unavoidable impurity elements. The yield strength is more than 1100MPa, the tensile strength is more than 1800MPa, and the elongation after fracture is more than 8%. The technical scheme has high C content, high carbon can seriously deteriorate the corrosion resistance, the existing size, form and distribution of carbide in a matrix are difficult to control, and the mechanical property can be seriously deteriorated when the size is large and appears on a grain boundary. The size and distribution of various precipitation phases are difficult to control in the two-stage aging process, the strengthening effect brought by the precipitation phases disappears after the precipitation phases grow up, the corrosion resistance is deteriorated, and the process is complicated.
Disclosure of Invention
The purpose of the invention is as follows: aiming at the problems of complex preparation process, low corrosion resistance and mechanical property thereof and the like of the existing ultrahigh-strength stainless steel, the invention provides 2700MPa grade high-plasticity toughness high-corrosion resistance maraging stainless steel and a preparation method thereof.
The technical scheme is as follows: the invention relates to a 2700MPa grade high-ductility high-corrosion-resistance maraging stainless steel which comprises the following components: the alloy material comprises, by mass, 3.0-6.0% of Co, 7.0-9.0% of Ni, 11.0-17.0% of Cr, 0.5-2.0% of Ti, 5.0-7.0% of Mo, 0.08-1.0% of Mn, 0.08-0.5% of Si, less than or equal to 0.02% of C, less than or equal to 0.003% of P, less than or equal to 0.003% of S, and the balance of Fe.
The invention principle and the component design basis of the 2700MPa grade high-ductility high-corrosion-resistance maraging stainless steel are as follows:
the invention principle is as follows: the stainless steel of the invention is not reinforced by carbon, the carbon is controlled at a very low level, and the toughness and the corrosion resistance of the stainless steel can be simultaneously improved. But the greatest problem with ultra-low carbon is low strength. By optimizing alloy elements, double vacuum melting and corresponding thermal mechanical treatment processes, a special structure is formed, and the structure consists of martensite laths and an amorphous layer modified by lath boundaries, wherein the martensite laths contain a plurality of nano-size dispersed precipitation phases. Ice water quenching and large cold rolling deformation can make the size of martensite laths fine and the dislocation density increased, and the fine martensite laths with high dislocation density can provide nucleation sites for precipitation phase bodies; at the same time, the high density of dislocations and defects between these nanoslabs lamellar structures concentrates a large amount of lattice strain, which generates a large amount of elastic strain energy due to the incoordination between atoms. In order to release the elastic strain energy between the atoms, they must interact with each other. Then, local crystal lattices are broken to disorder the atomic arrangement, and a nucleation region of an amorphous structure is generated. The attraction capacity of the lath boundary to atoms is strong, and elements are distributed to the lath boundary in the aging process, so that the disorder degree of the lath boundary is further increased, and the forming capacity of amorphous on the lath boundary is increased. During the deformation process of the composite structure, the extremely high yield strength is contributed by precipitation strengthening of multiple nano phases, on one hand, the nano-sized amorphous phase at the interface after yielding can promote dislocation proliferation to provide plasticity and strength, and simultaneously, the dislocation can be absorbed, the fracture caused by excessive dislocation entanglement and hardening is avoided, and the work hardening is further provided, so that the ultrahigh strength and the large plasticity can be obtained. During the thermomechanical treatment, reverse transformation austenite is also precipitated in the matrix, and the precipitated phases can delay the stress concentration of the material in the deformation process and ensure the plasticity.
The precipitated phase of the invention is rich in M formed by adjusting the contents of Ni, Ti, Mo and SiR 'phase of o, alpha' -Cr and Ni3The strength of the (Ti, Mo) nanophase is improved through cooperative strengthening, the three nano strengthening phases are mainly expressed in a cooperative precipitation relation, Ni-Ti-Mo-Si clusters which are fine in size and distributed in a dispersion mode are formed in the martensite laths or on dislocation at the early stage of aging, Mo and Si are gradually eliminated from the clusters along with the prolonging of aging time, and the nano-sized Ni is formed first3The (Ti, Mo) strengthening phase, after a period of heat preservation, Mo and Si are completely removed from Ni3The surface of Ti forms a Mo-rich R' phase to wrap it, Ni3The growth of Ti is inhibited, so that fine dispersion of a precipitated phase is ensured, and meanwhile, nano-sized alpha' -Cr is generated in the martensite lath; newly formed Mo-rich R' phase, Ni3Ti and alpha' -Cr together provide the matrix with higher strength. Dispersed Ni of DO24 structure3Ti can form reverse transformed austenite with nanometer size by the climbing of edge dislocation and the diffusion of Fe atoms by taking coherent strain energy of the interface of the Ti and the matrix as driving force, is uniformly distributed in the matrix, is easy to generate TRIP effect, and can effectively relieve stress concentration.
Meanwhile, in the process of distributing high-alloying elements such as Fe, Cr, Co, Ni and Mo to the lath boundary, the composition of the lath boundary is changed into a near-eutectic composition, the amorphous forming capability is improved, and the interface is changed from segregation to amorphousness. The amorphous phase can promote dislocation multiplication to provide plasticity and strength on one hand, can absorb dislocations, avoids excessive dislocation entanglement hardening to break, and further provides work hardening during uniform deformation, so that ultrahigh strength and large plasticity can be obtained.
The invention has the important innovation that the content of the expensive alloying element Co is greatly reduced, and the cost can be obviously reduced while the corrosion resistance is improved. Although the content of Co is designed at a lower level, the formation of Ni-Ti clusters is reduced, the ultrahigh strength is obtained by utilizing the synergistic strengthening of a plurality of nanophase through the combination of the optimization of alloy elements, double vacuum melting and corresponding thermal mechanical treatment processes; meanwhile, an amorphous layer is introduced into the lath boundary, and the lath boundary decorated by the amorphous layer promotes the dislocation multiplication and absorbs the dislocation, so that the large plasticity and the large processing hardening capacity are obtained. On the basis of innovation in the aspects of a strengthening mechanism, corresponding components, thermal mechanical treatment design and the like, the method is simple and controllable in process and effectively improves the mechanical property and the corrosion resistance.
The basis of component design is as follows: co is one of important elements to be considered in the invention, can improve Ms point and ensure that the matrix is martensite, but is a double-edged sword for martensite precipitation strengthening stainless steel. The addition of Co can reduce the solubility of Ti and Mo in the martensite matrix, form precipitates containing Mo or Ti, and further improve the strength. Co also hinders the recovery of dislocations, reduces the size of the precipitate phase and the matrix, and can produce a higher secondary hardening. However, addition of Co to martensitic stainless steel promotes spinodal decomposition of Cr, and the higher the content of Co, the greater the spinodal decomposition degree of Cr, which lowers the pitting corrosion resistance of the substrate. Meanwhile, the Co element is expensive, the content of Co is high, and the cost of the raw materials of the ultrahigh-strength stainless steel is high. Comprehensively considering that the mass percentage of Co should be controlled between 3.0 and 6.0 percent. E.g., 3.0%, 2.5%, 3.0%, 3.5%, 4.0%, 4.5%, 5.0%, 5.5%, 6.0%, etc.
Ni is an important element for forming intermetallic compounds, and is formed by forming B2-Ni (Ti, Mn) and eta-Ni in the early stage3(Ti, Mo) for strengthening matrix, eta-Ni3(Ti, Mo) is also the core of the Mo-R' rich phase nucleation; in addition, Ni can strengthen the matrix and provide certain ductility and toughness for the stainless steel; ni also improves the hardenability of martensite. Meanwhile, Ni is also a main element for forming reverse austenite, but too high content of Ni promotes the formation of residual austenite in the matrix, thereby affecting the strength of the stainless steel. Comprehensively considering that the mass percentage of Ni is controlled to be 6.0-10.0%. E.g., 6.0%, 6.5%, 7.0%, 7.5%, 8.0%, 8.5%, 9.0%, 9.5%, 10.0%, etc.
Mo is an important precipitation strengthening element. Mo is forming Mo-R' rich phase and Ni3One of the main elements of (Ti, Mo). The Mo-R' rich phase is formed after long-time aging and is wrapped by Ni3Ti forms a core-shell structure with fine dispersion distributionAnd the strength can be effectively improved. Mo is also an effective corrosion-resistant element, and the corrosion resistance of the material can be obviously improved by adding Mo. Meanwhile, Mo is also a forming element of ferrite, and the excessive content of Mo increases the precipitation tendency of delta ferrite, so that the content of Mo is increased, and the performance of the material is deteriorated. The mass percentage of Mo is comprehensively considered to be controlled to be 5.0-7.0%. E.g., 5.0%, 5.5%, 6.0%, 6.5%, 7.0%, etc.
Cr is an important element in stainless steel. In order to ensure the corrosion resistance of the stainless steel, the mass percentage of the stainless steel is generally more than 10 percent. However, Cr is a ferrite-forming element, and the content thereof is too high, so that the content of delta ferrite in the matrix is increased, and the toughness and corrosion resistance of the material are affected. Therefore, the mass percentage of Cr is controlled to be 11.0-17.0%. E.g., 11.0%, 11.5%, 12.0%, 12.5%, 13.0%, 13.5%, 14.0%, 14.5%, 15.0%, 15.5%, 16.0%, 16.5%, 17.0%, etc.
Si is one of important elements of the novel stainless steel, Si is one of main forming elements of the Mo-R 'rich phase, and the addition of Si can effectively promote the formation of the Mo-R' rich phase; si can also effectively inhibit the precipitation and growth of carbides in the martensite matrix in the tempering process, thereby preventing the occurrence of a Cr-poor area to reduce the corrosion resistance; however, too high a content of Si may seriously deteriorate the plasticity of the material. Comprehensively considering, the mass percentage of Si is controlled to be 0.08-0.50%. For example, 0.08%, 0.10%, 0.15%, 0.20%, 0.25%, 0.30%, 0.35%, 0.40%, 0.45%, 0.50%, etc.
Ti is a main strengthening phase forming element, which can form Ni-Ti clusters at the initial stage in preparation for the subsequent precipitation of a strengthening phase. When the content of Ti is too large, the tendency of precipitation of the precipitated phase at the boundary of the martensite lath becomes large, and when the content of the precipitated phase at the boundary of the martensite lath is too large, the precipitated phase is liable to develop into a crack source and propagate along the interface of the martensite lath, thereby initiating a quasi-cleavage crack. Comprehensively considering, the mass percentage of Ti should be controlled to be 0.5-2.0%. E.g., 0.5%, 1.0%, 1.5%, 2.0%, etc.
Mn is mainly participated in the precipitation of nano-phase to form Ni (Mn, Ti, Mo) intermetallic compounds, thereby replacing Ti and Mo elements in a small amount and reducing the cost. Mn is a main element affecting reverse austenite. However, too high Mn content causes serious segregation of the steel slab, large thermal stress and structural stress, and deterioration of weldability. Comprehensively considering, the mass percentage of Mn should be controlled to be 0.08-1.0%. For example, 0.08%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, etc.
C exists in the matrix as an impurity element in the stainless steel, and when the content of C is too high, MX or M is formed23C6Form carbides (M ═ Cr, Ti) which seriously retard the formation of reverse austenite, offset the gain of high dislocation density by cold rolling, and seriously deteriorate the toughness and corrosion resistance of steel when the size is too large, so that the C content is strictly controlled to 0.02% or less; p and S are impurity elements, and the performance of the stainless steel is seriously damaged by increasing the content of P and S, so the content is strictly controlled.
The invention relates to a preparation method of 2700MPa grade high-plasticity toughness high-corrosion-resistance maraging stainless steel, which comprises the following steps:
(1) proportioning alloy elements;
(2) carrying out vacuum smelting on the electrode by using a vacuum induction smelting furnace;
(3) vacuum consumable remelting;
(4) carrying out high-temperature flame equalizing treatment;
(5) forging or hot rolling cogging;
(6) cold rolling deformation;
(7) and (4) heat treatment.
After the alloy is smelted, cooling and forming to room temperature, cutting off a riser, removing the skin, and then entering a thermal mechanical treatment process. The structure with uniform and fine size can be obtained through hot rolling cogging, cold rolling deformation and heat treatment, so that the structure has higher strength, toughness and corrosion resistance.
In the step (1), the alloy elements are proportioned, according to the mass percentage of each element in the stainless steel, metal chromium, metal nickel, metal manganese, metal molybdenum, metal cobalt, metal titanium, iron silicon, and the balance of pure iron and inevitable impurities are selected, wherein the metals are high-purity metals and do not contain industrial waste metals.
In the step (2), the vacuum induction smelting furnace is adopted for vacuum smelting of the electrode, high vacuum smelting is adopted in the whole process, and the vacuum degree is below 0.1 Pa; adding pure iron, metallic nickel, metallic molybdenum and metallic cobalt into the furnace, adding metallic chromium and metallic titanium into the furnace from a high-level bin, and adding industrial silicon and metallic manganese into the furnace from an alloy bin. Adding materials along with the furnace, melting down, adding high-level bin metal, completely melting, performing deoxidation alloying, and finally adding alloy bin metal. In the smelting period, the refining temperature reaches 1550-1650 ℃, the refining time is not less than 60 minutes, and the stirring time is not less than 10 minutes; sampling in front of the furnace to analyze smelting components, and then adjusting the components according to the target designed by the claim 1; and after the target components are adjusted, pouring at the temperature of 1530-1550 ℃, and carrying out ordinary heat preservation on a riser.
In the step (3), the vacuum consumable remelting is carried out at a melting speed of 100-260 Kg/h, and the vacuum degree is kept at 10 in the remelting process-2Pa and below.
In the step (4), the high-temperature homogenizing treatment is carried out, heating is carried out in air, vacuum or protective atmosphere, the heating mode is furnace heating, the heating rate is 100-180 ℃/h, heat preservation is carried out for 4-8 h at 600-900 ℃, then the temperature is raised to 1100-1300 ℃, heat preservation is carried out for 20-50 h, and furnace cooling, air cooling or oil cooling is carried out until the room temperature is reached.
In the step (5), the forging or rolling may be performed by casting or rolling into a square ingot or a round ingot; the technological conditions of forging or hot rolling cogging are as follows: heating the casting blank to 1100-1300 ℃, preserving heat for 10-24 h, and then discharging for rolling; the forging or hot rolling starting temperature is more than or equal to 1100 ℃, the finish forging or rolling temperature is more than or equal to 950 ℃, the total hot rolling load of the plate is not less than 50%, the forging ratio of a forging billet is not less than 6, and after the forging or rolling deformation, the ice-water mixture is cooled.
In the step (6), the cold rolling deformation is performed, wherein the total reduction of the plate is 40-60%, and the pipes, rods, wires and sections are subjected to cold deformation by adopting a reciprocating pipe rolling, hole pattern rolling, universal rolling or drawing method, so as to obtain the required size and specification of the product.
In the step (7), the heat treatment process includes: and (5) aging treatment.
Further, in the step (7), the aging treatment: the temperature is 450-600 ℃, the aging time is 0.5-40h, and the steel plate is air-cooled or quenched to the room temperature.
Has the advantages that: compared with the prior art, the invention has the advantages that: (1) compared with other high-strength stainless steel, the stainless steel has lower content of noble metal and lower cost of raw materials (2) has extremely low carbon content or does not contain carbon (3), the 2700MPa grade high-plasticity toughness high-corrosion resistance maraging stainless steel has simple preparation method, can obtain the high-strength stainless steel through different heat treatment processes, has strong process controllability, and is easy to realize industrial production. Finally, the stainless steel with good corrosion resistance and excellent mechanical property is obtained.
Drawings
FIG. 1 is a stress-strain curve of example 1 after aging, with engineering strain on the abscissa and engineering stress on the ordinate;
FIG. 2 is an XRD plot of example 1 after aging with scan angle on the abscissa and diffraction intensity on the ordinate;
FIG. 3 is the transmission electron microscopy high resolution electron diffraction pattern after aging of example 1;
FIG. 4 is a metallographic morphology map of example 2 after aging;
FIG. 5 TEM image of example 2 after aging.
Detailed Description
The 2700MPa grade high ductility high corrosion resistant maraging stainless steel and the method for manufacturing the same according to the present invention will be further explained and illustrated with reference to the accompanying drawings and the specific examples, which, however, should not be construed to unduly limit the technical solutions of the present invention.
Example 1
Selecting pure iron, chromium metal, nickel metal, manganese metal, molybdenum metal, cobalt metal, titanium metal and iron silicon as raw materials, wherein the stainless steel comprises the following components in percentage by mass: 4.0 percent of Co, 13.0 percent of Cr, 0.5 percent of Mn, 6.0 percent of Mo, 8.0 percent of Ni, 0.5 percent of Si, 1.8 percent of Ti, less than or equal to 0.02 percent of C, less than or equal to 0.003 percent of P, less than or equal to 0.003 percent of S, and the balance of Fe. C. P, S is an inevitable impurity.
And preparing a billet by adopting vacuum melting in the whole process.
And (3) carrying out high-temperature flame equalizing treatment, heating in air in a mode of heating along with a furnace, keeping the temperature at 800 ℃ for 6h at a heating rate of 150 ℃/h, then heating to 1150 ℃ and keeping the temperature for 30h, and cooling to room temperature along with the furnace.
The technological conditions of hot rolling and cogging are as follows: heating the casting blank to 1100 ℃, preserving heat for 10 hours, and then discharging and rolling; the starting temperature of hot rolling is 1100 +/-20 ℃, the finishing temperature is more than or equal to 950 ℃, the total hot rolling amount of the plate is 60 percent, and the ice-water mixture is cooled.
The samples were cold rolled to a total reduction of 80%.
And (3) carrying out aging treatment on the cold-rolled sheet, wherein the aging temperature is 520 ℃, the aging time is 30h, and air cooling to room temperature.
The mechanical properties of example 1 are shown in Table 2, the average hardness is 578.2HV, the yield strength is 2291MPa, the tensile strength is 2737MPa, the elongation is 10.3%, and the pitting potential is 0.19VSCE. FIG. 1 is a stress-strain curve of example 1 after aging. FIG. 2 is an XRD diagram after aging of example 1, from which it is seen that a certain amount of reverse transformed austenite is precipitated. FIG. 3 is a transmission electron micrograph of the aged TEM sample of example 1 with amorphous diffraction rings at the martensite lath interface.
Example 2
Selecting pure iron, chromium metal, nickel metal, manganese metal, molybdenum metal, cobalt metal, titanium metal and iron silicon as raw materials, wherein the stainless steel comprises the following components in percentage by mass: 5.0 percent of Co, 12.0 percent of Cr, 1.0 percent of Mn, 7.0 percent of Mo, 9.0 percent of Ni, 0.4 percent of Si, 1.0 percent of Ti, less than or equal to 0.02 percent of C, less than or equal to 0.003 percent of P, less than or equal to 0.003 percent of S, and the balance of Fe. C. P, S is an inevitable impurity.
And preparing a billet by adopting vacuum melting in the whole process.
And (3) carrying out high-temperature tempering treatment, heating in air in a furnace at a heating rate of 100 ℃/h, keeping the temperature at 800 ℃ for 5h, then heating to 1100 ℃ and keeping the temperature for 20h, and cooling to room temperature in the furnace.
The technological conditions of hot rolling and cogging are as follows: heating the casting blank to 1250 ℃, preserving heat for 10 hours and then discharging and rolling; the starting temperature of hot rolling is 1100 +/-20 ℃, the finishing temperature is more than or equal to 950 ℃, the total rolling reduction of the plate is 50%, and the ice-water mixture is cooled.
The sheet was cold rolled with a total reduction of 85%.
And (3) carrying out aging treatment on the cold-rolled sheet, wherein the aging temperature is 480 ℃, the aging time is 10h, and air cooling to room temperature.
The mechanical properties of example 2 are shown in Table 2, the average hardness is 569.8HV, the yield strength is 2370MPa, the tensile strength is 2611MPa, the elongation is 9.8%, and the pitting potential is 0.24VSCE. FIG. 4 is the metallographic morphology after aging of example 2. FIG. 5 is an aged TEM image of example 2, from which it can be seen that there are dislocations in the martensite laths with a very high number density.
The test method for the corrosion resistance, the hardness and the tensile mechanical property of the 2700MPa grade high-ductility high-corrosion resistance maraging stainless steel in the embodiment is as follows.
(1) Hardness: the hardness test was carried out using an HVS-50 Vickers hardness tester with a load of 1Kg, and 5 points were hit and averaged, as shown in Table 2.
(2) Tensile mechanical properties: an electronic universal tester is adopted for tensile test, a rectangular sample with the nominal section size of 2-3 multiplied by 4 multiplied by 20.6mm is taken, and the average values of the tensile strength, the yield strength and the elongation of 3 samples treated in the same way are listed in table 2.
(3) Corrosion resistance
The test specimen was processed into a size of 10mm x 2mm and exposed to 1cm after being encapsulated with epoxy resin2And (4) performing a test, polishing the surface to 2000# by using sand paper, scrubbing by using alcohol to remove oil stains, cleaning by using deionized water, and drying for later use. The test solution was 0.1MNa2SO4+ xnacal (PH 3) experimental temperature 25 ℃. Electrochemical testing was performed using CHI660E electrochemical workstation. A common three-electrode system is adopted for carrying out electrochemical experiments, the experiment of ultrahigh-strength stainless steel is taken as a working electrode, a Pt sheet is taken as an auxiliary electrode, and a Saturated Calomel Electrode (SCE) is taken as a reference electrode. Prior to the electrochemical experiments, the samples were subjected to-1.2VSECThe applied potential of (2) is polarized for 5min at constant potential so as to remove the oxide film formed on the surface of the sample in the air. The system was stabilized for 30min and recording was started. The potentiodynamic polarization test has the scanning speed of 0.5mV/S and the scanning electrodeA potential region of-0.3V (vs. open circuit potential E)OC) 1.5V (vs. reference electrode potential E)R) The test was stopped after the current change was stable. The average values after 3 measurements are shown in Table 2.
TABLE 2 composition and hardness, tensile properties and pitting points of the examples
Note: the contents of C, P, S and the like in each example in Table 2 correspond to the elemental composition of stainless steel. Wherein C is less than or equal to 0.02%, P is less than or equal to 0.003%, S is less than or equal to 0.003%, which is not shown in Table 2. Bal denotes the balance.
In conclusion, the invention discloses 2700MPa grade high-plasticity toughness high-corrosion resistance maraging stainless steel and a preparation method thereof, wherein the stainless steel comprises the following components: the alloy material comprises, by mass, 3.0-6.0% of Co, 7.0-9.0% of Ni, 11.0-17.0% of Cr, 0.5-2.0% of Ti, 5.0-7.0% of Mo, 0.08-1.0% of Mn, 0.08-0.5% of Si, less than or equal to 0.02% of C, less than or equal to 0.003% of P, less than or equal to 0.003% of S, and the balance of Fe. According to the stainless steel, through the combination of optimization of alloy elements, double vacuum melting and corresponding thermal mechanical treatment processes, ultrahigh strength is obtained by utilizing the synergistic strengthening of multiple nanophase; meanwhile, an amorphous layer is introduced into the lath boundary, and the lath boundary decorated by the amorphous layer promotes the dislocation multiplication and absorbs the dislocation, so that the large plasticity and the large processing hardening capacity are obtained. Under the conditions that C is less than or equal to 0.02 percent and Co is not more than 6 percent, the stainless steel has the tensile strength as high as 2700MPa, the elongation as high as 10 percent and the pitting potential as high as 0.24VSCE(ii) a The method can be used for key structures of long blades for large-scale thermal power unit steam turbines, ships, ocean engineering and the like.
Claims (10)
1. A2700 MPa grade high plasticity and toughness high corrosion resistant maraging stainless steel is characterized by comprising the following components: according to mass percent, Co is 3.0-6.0%, Ni is 7.0-9.0%, Cr is 11.0-17.0%, Ti is 0.5-2.0%, Mo is 5.0-7.0%, Mn is 0.08-1.0%, Si is 0.08-0.5%, C is less than or equal to 0.02%, P is less than or equal to 0.003%, S is less than or equal to 0.003%, and the balance is Fe; the preparation method of the 2700MPa grade high-ductility high-corrosion-resistance maraging stainless steel comprises the following steps: (1) proportioning alloy elements, (2) carrying out vacuum smelting on electrodes in a vacuum induction smelting furnace; (3) vacuum consumable remelting; (4) carrying out high-temperature flame equalizing treatment; (5) forging or hot rolling cogging; (6) cold rolling deformation; (7) and (6) heat treatment.
2. A method of making a 2700MPa grade high ductility, high corrosion resistant maraging stainless steel according to claim 1, comprising the steps of:
(1) proportioning alloy elements;
(2) carrying out vacuum smelting on the electrode by using a vacuum induction smelting furnace;
(3) vacuum consumable remelting;
(4) carrying out high-temperature tempering treatment;
(5) forging or hot rolling cogging;
(6) cold rolling deformation;
(7) and (6) heat treatment.
3. The 2700MPa grade high-ductility high-corrosion resistant maraging stainless steel and the preparation method thereof according to claim 2, wherein in the step (1), the alloy elements are selected from chromium metal, nickel metal, manganese metal, molybdenum metal, cobalt metal, titanium metal and iron silicon metal according to the mass percentage of each element in the stainless steel, and the balance is pure iron and unavoidable impurities.
4. The 2700MPa grade high-ductility high-toughness high-corrosion-resistance maraging stainless steel and the preparation method thereof according to claim 2 are characterized in that in the step (2), a vacuum induction smelting furnace is adopted for vacuum smelting of the electrodes, high vacuum smelting is adopted in the whole process, and the vacuum degree is below 0.1 Pa; pure iron, metallic nickel, metallic molybdenum and metallic cobalt are added along with a furnace, metallic chromium and metallic titanium are added from a high-level stock bin, and industrial silicon and metallic manganese are added from an alloy stock bin. Adding materials along with a furnace, melting down, adding high-level bin metal, performing deoxidation alloying after complete melting, and finally adding alloy bin metal, wherein the melting period is that the refining temperature reaches 1550-1650 ℃, the refining time is not less than 60 minutes, and the stirring time is not less than 10 minutes; sampling in front of the furnace, analyzing smelting components, and then adjusting the components; after the target components are adjusted, pouring is carried out at the temperature of 1530-1550 ℃, and ordinary heat preservation is adopted for a riser.
5. The 2700MPa grade high-ductility high-corrosion resistant maraging stainless steel and the preparation method thereof as claimed in claim 2, wherein in the step (3), the vacuum consumable remelting is carried out at a melting speed of 100-260 Kg/h, and the vacuum degree is kept at 10 during the remelting process-2Pa and below.
6. The 2700MPa grade high-ductility high-corrosion-resistance maraging stainless steel and the preparation method thereof as claimed in claim 2, wherein in the step (4), the high-temperature tempering treatment is carried out, heating is carried out in air, vacuum or protective atmosphere, the heating mode is furnace heating, the heating rate is 100-180 ℃/h, the temperature is kept at 600-900 ℃ for 4-8 h, then the temperature is increased to 1100-1300 ℃ and kept for 20-50 h, and furnace cooling, air cooling or oil cooling is carried out until the room temperature.
7. The 2700MPa grade high ductility, high corrosion resistant maraging stainless steel and the method of manufacturing the same as set forth in claim 2, wherein the forging or rolling may be cast or rolled into a square ingot or a round ingot in size in step (5); the technological conditions of forging or hot rolling cogging are as follows: heating the casting blank to 1100-1300 ℃, preserving heat for 10-24 h, and then discharging for rolling; the forging or hot rolling starting temperature is more than or equal to 1100 ℃, the finish forging or rolling temperature is more than or equal to 950 ℃, the total hot rolling load of the plate is not less than 50%, the forging ratio of a forging billet is not less than 6, and after the forging or rolling deformation, the ice-water mixture is cooled.
8. The 2700MPa grade high-ductility high-corrosion-resistance maraging stainless steel and the preparation method thereof of claim 2, wherein in the step (6), the cold rolling deformation is carried out, the total reduction of the cold rolling of the plate is not less than 65%, and the cold deformation of the tube, the bar, the wire and the section is carried out by adopting a reciprocating tube rolling method, a hole rolling method, a universal rolling method or a drawing method, so as to obtain the required size and specification of the product.
9. The 2700MPa grade high ductility, toughness and corrosion resistant maraging stainless steel and the method of manufacturing the same as set forth in claim 2, wherein the heat treatment process in the step (7) comprises: and (5) aging treatment.
10. The 2700MPa grade high-ductility-toughness high-corrosion-resistance maraging stainless steel and the preparation method thereof of claim 9, wherein the aging treatment temperature is 450-600 ℃, the aging time is 0.5-500h, and the stainless steel is air-cooled or quenched to room temperature.
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Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62142722A (en) * | 1985-12-18 | 1987-06-26 | Nippon Steel Corp | Manufacture of high tension steel superior in weldability |
| CN1630732A (en) * | 2000-11-17 | 2005-06-22 | 伊菲尤金精度公司 | Maraging steel and process for manufacturing a strip or a part cut out of a strip of cold-rolled maraging steel |
| CN101050509A (en) * | 2007-05-17 | 2007-10-10 | 钢铁研究总院 | Martensite ageing stainless steel with high strength and high toughness |
| CN101886228A (en) * | 2009-05-13 | 2010-11-17 | 中国科学院金属研究所 | Low carbon martensite aged stainless steel with high strength high toughness and high decay resistance performances |
| US20100308505A1 (en) * | 2009-06-05 | 2010-12-09 | Edro Specialty Steels, Inc. | Plastic injection mold of low carbon martensitic stainless steel |
| CN102251191A (en) * | 2011-07-21 | 2011-11-23 | 重庆仪表材料研究所 | Martensite stainless steel and preparation method for flat strip of martensite stainless steel |
| CN104087734A (en) * | 2014-07-11 | 2014-10-08 | 江苏润源控股集团有限公司 | Method for preparing high-performance maraging-steel steel belt |
| CN106536762A (en) * | 2014-07-16 | 2017-03-22 | 日立金属株式会社 | Production method for maraging steel and production method for maraging steel consumable electrode |
| CN106756583A (en) * | 2015-11-25 | 2017-05-31 | 中国科学院金属研究所 | A kind of ultra-high-strength/tenacity Maraging steel and its preparation method and application |
| CN107254642A (en) * | 2017-06-02 | 2017-10-17 | 浙江大学 | A kind of martensite aged stainless steel and preparation method thereof |
| CN113046642A (en) * | 2021-03-11 | 2021-06-29 | 哈尔滨工程大学 | Low-cost high-strength high-corrosion-resistance stainless steel and preparation method thereof |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101994066B (en) * | 2009-08-27 | 2012-07-04 | 中国科学院金属研究所 | Deformation induced maraging stainless steel and machining process thereof |
| CN102492894B (en) * | 2011-12-30 | 2016-02-17 | 重庆材料研究院 | The corrosion-resistant martensitic steel of high-dimensional stability and steel structure material preparation method thereof |
| CN106119736B (en) * | 2016-05-26 | 2018-07-27 | 中国科学院金属研究所 | A kind of martensite aged stainless steel |
| CN107653421B (en) * | 2016-07-26 | 2019-12-10 | 中国科学院金属研究所 | Seawater corrosion resistant ultrahigh-strength maraging stainless steel |
-
2021
- 2021-08-25 CN CN202110984362.9A patent/CN113774289A/en active Pending
-
2022
- 2022-04-07 CN CN202210364161.3A patent/CN114717487B/en active Active
Patent Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62142722A (en) * | 1985-12-18 | 1987-06-26 | Nippon Steel Corp | Manufacture of high tension steel superior in weldability |
| CN1630732A (en) * | 2000-11-17 | 2005-06-22 | 伊菲尤金精度公司 | Maraging steel and process for manufacturing a strip or a part cut out of a strip of cold-rolled maraging steel |
| CN101050509A (en) * | 2007-05-17 | 2007-10-10 | 钢铁研究总院 | Martensite ageing stainless steel with high strength and high toughness |
| CN101886228A (en) * | 2009-05-13 | 2010-11-17 | 中国科学院金属研究所 | Low carbon martensite aged stainless steel with high strength high toughness and high decay resistance performances |
| US20100308505A1 (en) * | 2009-06-05 | 2010-12-09 | Edro Specialty Steels, Inc. | Plastic injection mold of low carbon martensitic stainless steel |
| CN102251191A (en) * | 2011-07-21 | 2011-11-23 | 重庆仪表材料研究所 | Martensite stainless steel and preparation method for flat strip of martensite stainless steel |
| CN104087734A (en) * | 2014-07-11 | 2014-10-08 | 江苏润源控股集团有限公司 | Method for preparing high-performance maraging-steel steel belt |
| CN106536762A (en) * | 2014-07-16 | 2017-03-22 | 日立金属株式会社 | Production method for maraging steel and production method for maraging steel consumable electrode |
| CN106756583A (en) * | 2015-11-25 | 2017-05-31 | 中国科学院金属研究所 | A kind of ultra-high-strength/tenacity Maraging steel and its preparation method and application |
| CN107254642A (en) * | 2017-06-02 | 2017-10-17 | 浙江大学 | A kind of martensite aged stainless steel and preparation method thereof |
| CN113046642A (en) * | 2021-03-11 | 2021-06-29 | 哈尔滨工程大学 | Low-cost high-strength high-corrosion-resistance stainless steel and preparation method thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116377314A (en) * | 2023-06-05 | 2023-07-04 | 成都先进金属材料产业技术研究院股份有限公司 | Martensitic heat-resistant steel for gas turbine and smelting method thereof |
| CN116377314B (en) * | 2023-06-05 | 2023-10-27 | 成都先进金属材料产业技术研究院股份有限公司 | Martensitic heat-resistant steel for gas turbine and smelting method thereof |
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