CN114717486A - Ultra-high-strength high-performance maraging stainless steel and warm rolling preparation method thereof - Google Patents
Ultra-high-strength high-performance maraging stainless steel and warm rolling preparation method thereof Download PDFInfo
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Abstract
The invention discloses a super-high strength high performance maraging stainless steel and a warm rolling preparation method thereof, wherein the stainless steel comprises the following components: the alloy material comprises, by mass%, 2.0-5.0% of Co, 7.0-9.0% of Ni, 11.0-13.0% of Cr, 0.2-1.5% of Ti, 4.0-6.0% of Mo, 0.05-1.5% of Mn, 0.05-0.5% 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 successfully obtains the stainless steel with excellent performance by regulating and controlling the distribution, the size and the volume fraction of the nano-scale precipitation phase in a matrix and the reverse transformation austenite, and the stainless steel has the tensile strength as high as 2.1GPa, the elongation as high as 13 percent and the pitting potential as high as 0.18V under the conditions that the C is less than or equal to 0.02 percent and the Co is not more than 5 percentSCE(ii) a The method can be used for key structures of ships, ocean engineering, aerospace engineering and the like.
Description
Technical Field
The invention relates to ultrahigh-strength high-performance maraging stainless steel and a warm rolling 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 stainless steel has the strength of maraging reinforced steel and the corrosion resistance of 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 1 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 1 commercial high strength stainless steel compositions and properties thereof currently on the market
The high content of Co ensures that the mechanical property of the high-strength stainless steel is 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, Co is added in an appropriate amount.
Aiming at the characteristic of difficult cold deformation of an ultrahigh-strength stainless steel hot rolled plate, the warm rolling process is adopted in the preparation process, the deformation resistance of the material is small, the load of a rolling mill is reduced, the abrasion of a roller is reduced, the subgrain is further crushed and refined in the rolling process, and more positions are provided for nucleation of a precipitated phase; the innovation of the invention is that the refined martensite lath and the effective grain size are controlled by the alloy components, the double vacuum melting process and the thermal mechanical treatment process, the precipitation kinetics of the nano-phase and the reverse transformation austenite nucleation and growth kinetics are improved, and the size, distribution and volume fraction of the nano-phase precipitated in the martensite matrix and the reverse transformation austenite are controlled; the nanometer phase and dislocation act to control strengthening and reverse transformed austenite toughening, and the improvement of mechanical property is realized. Meanwhile, on one hand, carbon strengthening is replaced 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 through 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 Ferrum 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%. 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 7.5-13.0%, and the pitting potential Epit is more than or equal to 0.15V. The invention purpose, strengthening mechanism and preparation process of the invention are completely different compared with the invention, which is essentially different from the invention.
Disclosure of Invention
The purpose of the invention is as follows: the invention provides a maraging stainless steel with ultrahigh strength and high performance and a preparation method thereof, aiming at the problems of difficult cold deformation of an ultrahigh strength stainless steel hot rolled plate, higher raw material cost, complex preparation process, lower corrosion resistance and mechanical property thereof and the like.
The technical scheme is as follows: the invention relates to an ultra-high strength high performance maraging stainless steel which comprises the following components: the alloy material comprises, by mass, 2.0-5.0% of Co, 7.0-9.0% of Ni, 11.0-13.0% of Cr, 0.2-1.5% of Ti, 4.0-6.0% of Mo, 0.05-1.5% of Mn, 0.05-0.5% 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 ultra-high-strength high-performance maraging stainless steel are as follows:
the invention principle is as follows: the size of laths and subgrains of martensite is controlled by optimizing alloy elements, double-vacuum melting and corresponding thermo-mechanical treatment processes, the regulation and control of precipitation strengthening nano-phases are realized by a warm rolling process, and reverse transformation austenite is introduced into a matrix. The stainless steel with excellent performance is successfully obtained by regulating and controlling the distribution, the size and the volume fraction of the nano-scale precipitated phase in a matrix and the reversed transformed austenite. The ice-water quenching cooling leads to fine martensite laths and increased dislocation density, the fine martensite laths provide nucleation sites for precipitation phase and membranous metastable reverse transformed austenite, and the higher dislocation density adds element distribution channels for the reverse transformed austenite, and the reverse austenite generated by the method is easier to generate TRIP (transformation Induced plasticity) effect when being loaded, so that the plasticity and the strength can be obviously improved. The billet is subjected to dynamic recovery recrystallization in the warm rolling process, the subgrain structure is refined, the effective grain size is reduced, and the fine structure ensures the strong plasticity of the material.
The precipitated phase of the invention is formed by adjusting the contents of Ni, Ti, Mo and Si to form an R 'phase rich in Mo, 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.
Simultaneously, Ni of DO24 structure is dispersed and distributed3The reverse transformed austenite with a film-shaped structure and dispersed distribution can be formed by the climb of edge dislocation and the diffusion of Fe atoms by taking coherent strain energy of a matrix interface as driving force of Ti, the energy required by reverse austenite nuclei is greatly reduced by high dislocation density and fine martensite laths, and a diffusion channel is provided for the growth of the reverse austenite by high dislocation density. These film-like componentsThe reversed austenite of the cloth has a Mo-rich nano precipitated phase, so that the work hardening capacity of the material can be greatly improved in the plastic deformation process, and the yield ratio of the ultrahigh-strength steel can be effectively reduced.
Aiming at the characteristic of difficult cold deformation of an ultrahigh-strength stainless steel hot rolled plate, the warm rolling process is adopted in the preparation process, the deformation resistance of the material is small, the load of a rolling mill is reduced, the abrasion of a roller is reduced, the subgrain is further crushed and refined in the rolling process, and more positions are provided for nucleation of a precipitated phase; another important innovation is that the carbon content and the content of the expensive alloying element Co are greatly reduced, and the corrosion resistance is improved, and the cost can be obviously reduced. Although the low Co content design reduces the forming capability of the Ni-Ti cluster, the regulation and control of the precipitation strengthening nano-phase are realized by optimizing alloy elements, double vacuum melting and corresponding thermo-mechanical treatment processes, and reverse transformed austenite is introduced into the matrix. The distribution, size and volume fraction of the nano-scale precipitation phase in the matrix and the reverse transformation austenite are regulated and controlled, so that the strength and the plasticity and toughness are obviously improved. On the basis of innovation in the aspects of strengthening mechanism, corresponding components, thermal mechanical treatment design, thermal treatment and the like, the mechanical property and the corrosion resistance are effectively improved on the basis of simple and controllable process and cost reduction.
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 is controlled to be 2.0-5.0%. E.g., 2.0%, 2.5%, 3.0%, 3.5%, 4.0%, 4.5%, 5.0%, 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 nuclei; 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 7.0-9.0%. E.g., 7.0%, 7.5%, 8.0%, 8.5%, 9.0%, 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 distribution, and 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 4.0-6.0%. E.g., 4.0%, 4.5%, 5.0%, 5.5%, 6.0%, 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 11.0-13.0%. E.g., 11.0%, 11.5%, 12.0%, 12.5%, 13.0%, 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, so that the Cr-poor area is prevented from appearing 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 0.05-0.5%. E.g., 0.05%, 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 0.2-1.5%. E.g., 0.2%, 0.5%, 1.0%, 1.5%, etc.
Mn mainly participates in the precipitation of a nano phase to form an intermetallic compound of Ni (Mn, Ti and Mo), so that Ti and Mo elements can be replaced by a small amount, and the cost is reduced. 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 0.05-1.5%. E.g., 0.05%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 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 warm rolling preparation method of the ultra-high strength and high performance maraging stainless steel comprises the following steps:
(1) proportioning alloy elements;
(2) carrying out vacuum smelting on the electrode by using a vacuum induction smelting furnace;
(3) remelting at vacuum consumable;
(4) carrying out high-temperature flame equalizing treatment;
(5) forging or hot rolling cogging;
(6) warm rolling deformation;
(7) and (6) 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, warm 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 finish rolling temperature is more than or equal to 950 ℃, the total hot rolling amount of the plate is not less than 50%, and the ice-water mixture is cooled to room temperature.
In the step (6), the warm rolling deformation process conditions are as follows: and (3) preserving the heat at 500-700 ℃ for 30-300 min, wherein the total rolling reduction of the plate is not less than 50%.
In the step (7), the heat treatment process includes: and (5) aging treatment.
Further, in step (7), the aging treatment: the temperature is 450-600 ℃, the aging time is 0.5-500h, 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 high-strength martensitic aging stainless steel has the advantages of low content of noble metal and low cost of raw materials (2) no carbon or extremely low carbon content in the stainless steel (3) adoption of a warm rolling process, small deformation resistance, reduced load of a rolling mill and reduced abrasion of a roller (4) simple preparation method of the high-strength high-performance martensitic aging stainless steel and the warm rolling thereof, capability of obtaining the high-strength stainless steel through different heat treatment processes, strong process controllability and easiness in realization of industrial production. Finally, the stainless steel with good corrosion resistance and excellent mechanical property is obtained.
Drawings
FIG. 1 stress strain plot after aging for example 1; in the figure, the abscissa is engineering strain and the ordinate is engineering stress;
FIG. 2 is a metallographic morphology map of example 2 after aging;
FIG. 3 example 2 shows a reversed austenitic transmission electron microscope high-angle annular dark field pixel distribution diagram.
Detailed Description
The ultra-high strength and high performance maraging stainless steel and the warm rolling method for manufacturing the same according to the present invention will be further explained and illustrated with reference to the accompanying drawings and 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, 11.0 percent of Cr, 0.1 percent of Mn, 5.0 percent of Mo, 8.0 percent of Ni, 0.1 percent of Si, 0.5 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 700 ℃ for 4h at the heating rate of 180 ℃/h, then heating to 1150 ℃ and keeping the temperature for 25h, 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 1200 ℃, preserving heat for 10 hours, and then discharging and rolling; the starting temperature of hot rolling is 1150 +/-20 ℃, the finishing temperature is more than or equal to 950 ℃, the total rolling reduction of the plate is 60 percent, and the ice-water mixture is cooled.
The process condition of warm rolling of the plate is that the temperature is kept at 500 ℃ for 30min, and the total reduction of the plate is 60%.
And (3) carrying out aging treatment on the warm-rolled plate, wherein the aging temperature is 480 ℃, the aging time is 5h, and air cooling to room temperature.
The mechanical properties of example 1 are shown in Table 2, the average hardness is 503.1HV, the yield strength is 2000MPa, the tensile strength is 2115MPa, the elongation is 10%, and the pitting potential is 0.18VSCE. FIG. 1 is a graph of stress strain after aging for example 1.
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: 4.0 percent of Co, 11.0 percent of Cr, 0.3 percent of Mn, 5.5 percent of Mo, 8.0 percent of Ni, 0.2 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 flame equalizing treatment, heating in air in a mode of heating along with a furnace, keeping the temperature at 700 ℃ for 5h at the heating rate of 180 ℃/h, then heating to 1200 ℃ 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 1200 ℃, preserving heat for 20 hours, and then discharging and rolling; the starting temperature of hot rolling is 1150 +/-20 ℃, the finishing temperature is more than or equal to 950 ℃, the total rolling reduction of the plate is 70 percent, and the ice-water mixture is cooled.
The process condition of warm rolling of the plate is that the temperature is preserved for 30min at 550 ℃, and the total reduction of the plate is 65%.
And (3) carrying out aging treatment on the warm-rolled plate, wherein the aging temperature is 500 ℃, the aging time is 5h, and air cooling to room temperature.
The mechanical properties of example 2 are shown in Table 2, the average hardness is 508.6HV, the yield strength is 2010MPa, the tensile strength is 2150MPa, the elongation is 9.5%, and the pitting potential is 0.16VSCE. FIG. 2 is a metallographic morphology graph after aging in example 2. FIG. 3 is the element distribution diagram of the high-angle annular dark field image of the reverse austenite transmission electron microscope in example 2, wherein a large amount of membranous reverse transformed austenite is found, precipitation of precipitated phases exists in the reverse transformed austenite, and simultaneously, three precipitated phases also exist in martensite.
The test methods for the corrosion resistance, hardness and tensile mechanical properties of the ultra-high strength high performance maraging stainless steel in the above examples are 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# with sand paper, scrubbing with alcohol to remove oil stains, cleaning with deionized water, and drying for later use. The experimental solution was 0.1MNa2SO4+ xnacal (PH 3) experimental temperature 25 ℃. Electrochemical testing was performed using the 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 stable for 30min and recording was started. The potentiodynamic polarization test has a scanning rate of 0.5mV/S and a scanning potential area of-0.3V (vs. open circuit potential E)OC) 1.5V (vs. reference electrode potential E)R) And stopping the test after the current change is 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.
The invention discloses a super-high strength high performance maraging stainless steel and a warm rolling preparation method thereof, wherein the stainless steel comprises the following components: the alloy material comprises, by mass%, 2.0-5.0% of Co, 7.0-9.0% of Ni, 11.0-13.0% of Cr, 0.2-1.5% of Ti, 4.0-6.0% of Mo, 0.05-1.5% of Mn, 0.05-0.5% 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. Aiming at the characteristic of difficult cold deformation of an ultrahigh-strength stainless steel hot rolled plate, the preparation process adopts a warm rolling process, the deformation resistance of the material is small, and the subgrain is crushed and refined to provide more positions for nucleation of a precipitated phase; realizes the regulation and control of precipitation strengthening nanophase by optimizing alloy elements, double vacuum melting and corresponding thermal mechanical treatment process, and introduces the precipitation strengthening nanophase into a matrixAnd (4) reversely transforming austenite. The stainless steel with excellent performance is successfully obtained by regulating and controlling the distribution, size and volume fraction of the nano-scale precipitated phase in a matrix and reverse transformed austenite. The stainless steel has the tensile strength up to 2.1GPa, the elongation up to 13 percent and the pitting potential up to 0.18V under the conditions that the C is less than or equal to 0.02 percent and the Co is not more than 5 percentSCE(ii) a The method can be used for key structures of ships, ocean engineering, aerospace engineering and the like.
Claims (10)
1. The ultra-high strength high performance maraging stainless steel is characterized by comprising the following components: according to mass percent, Co is 2.0-5.0%, Ni is 7.0-9.0%, Cr is 11.0-13.0%, Ti is 0.2-1.5%, Mo is 4.0-6.0%, Mn is 0.05-1.5%, Si is 0.05-0.5%, 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 ultra-high-strength high-performance maraging stainless steel and the warm rolling preparation method thereof comprise the following steps: (1) alloy element proportioning (2) carrying out vacuum smelting on an electrode 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) warm rolling deformation; (7) and (4) heat treatment.
2. A warm rolling method for producing an ultra-high strength high performance 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 flame equalizing treatment;
(5) forging or hot rolling cogging;
(6) warm rolling deformation;
(7) and (6) heat treatment.
3. The ultra-high strength high performance maraging stainless steel and the warm rolling preparation method thereof according to claim 2, wherein in the step (1), the alloy element proportion is that metal chromium, metal nickel, metal manganese, metal molybdenum, metal cobalt, metal titanium and iron silicon are selected according to the mass percentage of each element in the stainless steel, and the balance is pure iron and unavoidable impurities.
4. The ultra-high strength high performance maraging stainless steel and the warm rolling preparation method thereof according to claim 2, wherein in the step (2), the electrode is smelted in vacuum by using a vacuum induction smelting furnace, 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 a furnace, adding metallic chromium and metallic titanium into a high-position stock bin, adding industrial silicon and metallic manganese into an alloy stock bin, adding the high-position stock bin metal into the furnace after the industrial silicon and the metallic manganese are melted down, performing deoxidation alloying after the high-position stock bin metal is completely melted, and finally adding the alloy stock bin metal into the furnace, wherein the smelting 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 10-15 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 ultra-high strength high performance maraging stainless steel and the warm rolling preparation method thereof according to 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 ultra-high strength and high performance maraging stainless steel and the warm rolling preparation method thereof as claimed in claim 2, wherein in step (4), the high temperature is homogenized, the steel is heated 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 the steel is furnace cooled, air cooled or oil cooled to room temperature.
7. The ultra-high strength high performance maraging stainless steel and the warm rolling preparation method thereof according to claim 2, wherein in the step (5), the forging or rolling may be cast or rolled into a square ingot or a round ingot in size; 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 starting temperature of forging or hot rolling is more than or equal to 1100 ℃, the final forging or rolling temperature is more than or equal to 950 ℃, the total hot rolling quantity of the plate is not less than 50%, the forging ratio of a forging billet is not less than 6, and after forging or rolling deformation, the ice-water mixture is cooled.
8. The ultra-high strength high performance maraging stainless steel and the warm rolling preparation method thereof according to claim 2, wherein in the step (6), the process conditions of the warm rolling deformation are as follows: and (3) preserving the heat at 500-700 ℃ for 30-300 min, wherein the total rolling reduction of the plate is not less than 50%.
9. The ultra-high strength high performance maraging stainless steel and the warm rolling preparation method thereof according to claim 2, wherein in the step (7), the heat treatment process comprises: and (5) aging treatment.
10. The ultra-high strength high performance maraging stainless steel and the warm rolling preparation method thereof according to claim 9, wherein the aging treatment temperature is 450-600 ℃, the aging time is 0.5-500h, and the steel is air-cooled or quenched to room temperature.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101205595A (en) * | 2006-12-22 | 2008-06-25 | 宝山钢铁股份有限公司 | Tough ultra-strength stainless steel and method for manufacturing the same |
| CN104911501A (en) * | 2015-05-25 | 2015-09-16 | 西安交通大学 | Super-strength high-carbon potential dislocation martensitic steel, and preparation method thereof |
| CN111218618A (en) * | 2020-02-27 | 2020-06-02 | 钢铁研究总院 | Hydrogen embrittlement resistant, high strength and toughness stainless steel bar for fastener and method of making same |
| CN112453101A (en) * | 2020-11-10 | 2021-03-09 | 华能国际电力股份有限公司 | Forming preparation process of large-caliber thick-wall pipe made of iron-based high-temperature alloy |
| CN113046654A (en) * | 2021-03-11 | 2021-06-29 | 哈尔滨工程大学 | High-plasticity high-strength high-corrosion-resistance 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 (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE518600C2 (en) * | 1999-11-17 | 2002-10-29 | Sandvik Ab | automotive Suppliers |
| 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 |
| CN110066964B (en) * | 2019-04-09 | 2021-06-01 | 东北大学 | Ultrahigh-strength medium manganese steel and warm rolling preparation method thereof |
-
2021
- 2021-08-25 CN CN202110982723.6A patent/CN113667905A/en active Pending
-
2022
- 2022-04-07 CN CN202210364156.2A patent/CN114717486B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101205595A (en) * | 2006-12-22 | 2008-06-25 | 宝山钢铁股份有限公司 | Tough ultra-strength stainless steel and method for manufacturing the same |
| CN104911501A (en) * | 2015-05-25 | 2015-09-16 | 西安交通大学 | Super-strength high-carbon potential dislocation martensitic steel, and preparation method thereof |
| CN111218618A (en) * | 2020-02-27 | 2020-06-02 | 钢铁研究总院 | Hydrogen embrittlement resistant, high strength and toughness stainless steel bar for fastener and method of making same |
| CN112453101A (en) * | 2020-11-10 | 2021-03-09 | 华能国际电力股份有限公司 | Forming preparation process of large-caliber thick-wall pipe made of iron-based high-temperature alloy |
| CN113046654A (en) * | 2021-03-11 | 2021-06-29 | 哈尔滨工程大学 | High-plasticity high-strength high-corrosion-resistance 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 |
Non-Patent Citations (1)
| Title |
|---|
| 王顺兴, 哈尔滨工业大学出版社 * |
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