CN117845137A - Mn-Si-V-Ti-Nb-Cr multi-element alloyed hot rolled wire rod and preparation method thereof - Google Patents
Mn-Si-V-Ti-Nb-Cr multi-element alloyed hot rolled wire rod and preparation method thereof Download PDFInfo
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Abstract
The invention relates to an Mn-Si-V-Ti-Nb-Cr multi-element alloying hot rolled wire rod and a preparation method thereof, belongs to the technical field of wire rods for prestressed steel, and solves the problems of low tensile strength, low area shrinkage and insufficient strong plasticity matching and stress corrosion resistance of a prestressed steel strand prepared subsequently in the prior art. The alloy components of the hot rolled wire rod are as follows by mass percent: c:0.75 to 0.90 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr: less than or equal to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities. The tensile strength of the hot rolled wire rod disclosed by the invention reaches 1150-1350 MPa, the reduction of area is more than or equal to 35%, and the preparation process is simple and suitable for large-scale manufacturing.
Description
Technical Field
The invention relates to the technical field of wire rods for prestressed steel, in particular to an Mn-Si-V-Ti-Nb-Cr multi-element alloyed hot rolled wire rod and a preparation method thereof.
Background
The prestressed steel strand is widely applied to the fields related to national life such as traffic construction, water conservancy and hydropower, energy and the like. At present, 1860 MPa-level prestressed steel strands are most widely used. In recent years, corresponding standards such as GB/T5224-2023 steel stranded wires for prestressed concrete, JG/T369-2012 slow bonding prestressed steel stranded wires, JG/T161-2016 unbonded prestressed steel stranded wires and the like are additionally provided with 1960 MPa-level prestressed steel stranded wires with higher strength. JGJ 369-2016 "design Specification of prestressed concrete Structure" clearly indicates that a steel strand with the tensile strength of 1960MPa level can be used as post-tensioned prestressed reinforcement. In addition to the development direction of ultra-high strength and light weight, the 1860 MPa-grade and above high-strength prestressed steel wire has high ductility, and the total maximum force elongation is remarkably higher than 3.5 percent specified in GB/T5224-2023, so that the prestressed steel wire has higher tensioning redundancy in construction and higher bearing and light weight effects are realized. Therefore, the high strength and high plasticization of the prestressed steel strands are also important development directions.
The wire rod (most of hot rolled wire rods) for the prestressed steel is a main preparation raw material/process product of the prestressed steel strand, and the mechanical property and the area reduction rate of the wire rod are closely related to the property of the final steel strand. At present, a 1860 MPa-level prestressed steel strand is prepared by a common 82B hot-rolled wire rod, but the common 82B hot-rolled wire rod has the defects of low tensile strength (1130-1250 MPa), low area reduction rate (30% -37%), and the like, so that the problem of insufficient redundancy of strength and ductility (maximum total elongation) of the subsequently prepared prestressed steel strand is caused. The prestress steel strand with the diameter of more than 1860MPa is prepared by the 82B hot rolled wire rod with larger diameter specification, namely high strengthening is realized by large deformation drawing, but the prepared prestress steel strand has insufficient ductility and stress corrosion resistance. The strength and plasticity of the common 82B wire rod can be improved through off-line salt bath heat treatment, but the complexity and cost of the preparation process of the pre-stress steel strand above 1860MPa level are increased, and the stress corrosion resistance is still insufficient.
Disclosure of Invention
In view of the above analysis, the embodiment of the invention aims to provide a Mn-Si-V-Ti-Nb-Cr multi-element alloyed hot rolled wire rod and a preparation method thereof, which are used for solving the problems of insufficient tensile strength and lower area reduction rate of the existing hot rolled wire rod for prestressing, and further improving the strength and ductility of the prestressing steel strand prepared later and the stress corrosion resistance.
The invention discloses a Mn-Si-V-Ti-Nb-Cr multi-element alloyed hot rolled wire rod, which comprises the following alloy components in percentage by mass: c:0.75 to 0.90 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr: less than or equal to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities.
Preferably, the alloy components of the hot rolled wire rod are as follows by mass percent: c:0.80 to 0.90 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr:0.10 to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities.
Specifically, the proportion of the microalloy of V, ti and Nb in the hot rolled wire rod is satisfied (V is 0.04-0.06%, ti is 0.010-0.025%, nb is 0.01-0.03%) or (V is 0.07-0.10%, ti is 0.010-0.025%, nb is less than 0.01%).
Specifically, the diameter of the hot rolled wire rod is 12.5-14 mm, the microstructure is complete lamellar pearlite, and no network cementite exists.
Specifically, the tensile strength of the hot rolled wire rod is 1150-1350 MPa, and the area shrinkage is more than or equal to 35%.
The invention also discloses a preparation method of the hot rolled wire rod, which comprises the following steps:
s1: batching according to alloy composition, and smelting and casting to obtain a casting blank;
s2: homogenizing the casting blank, namely heating to the austenite homogenizing temperature and preserving heat;
s3: continuously rolling the heat-preserving casting blank after descaling until reaching the target diameter to obtain a semi-finished product wire rod;
s4: and (3) curling and air-cooling the semi-finished wire rod to obtain the finished hot rolled wire rod.
Specifically, the austenite homogenization temperature in the step S2 is 1180-1250 ℃, and the heat preservation time is 0.5-3 h.
Preferably, when the Nb content in the alloy is 0.01% -0.03%, the austenite homogenization temperature is 1200-1250 ℃.
Specifically, the air cooling speed after the hot rolling in the step S4 and before the hot rolling reaches 500 ℃ is 1.5 ℃/S-3.5 ℃/S.
The invention also discloses a prestress steel strand, which is prepared from the hot rolled wire rod or the hot rolled wire rod prepared by the preparation method through pickling, cold drawing, stranding and stabilizing heat treatment.
Compared with the prior art, the invention has at least one of the following beneficial effects:
1. the hot rolled wire rod disclosed by the invention has high tensile strength and high reduction of area. In the wire rod, cr is added as an alloy element on the basis of Mn-Si main alloying, so that the interlayer spacing of pearlite sheets can be thinned, the mechanical strength of the alloy is improved, and the wire rod is particularly beneficial to manufacturing high-strength prestressed steel/steel twisted wires; the V-Ti (-Nb) strong carbide forming element microalloy design is adopted, and the MX type second phase particles are separated out in a grading way to refine austenite grains, so that the size of pearlite clusters is further refined, the orientation diversity of lamellar layers is increased, the area shrinkage is improved, and the drawing performance is improved; wherein Nb is used as an optional microalloying element and is added in a matching way according to the V content in the alloy. The V, ti and Nb strong carbide forming elements have the following fractional precipitation characteristics. Ti fixes N and is almost completely precipitated as TiN or Ti (C, N) refined austenite grains homogenized before hot rolling, and Ti (C, N) may contain a small amount of Nb or V. Nb is partially separated out in the hot rolling process, and NbC particles and solid-solution Nb act together to refine austenite grains, so that austenite deformation energy storage is improved, pearlite transformation driving force is improved, and meanwhile, pearlite clusters and lamellar spacing are refined; the incompletely precipitated Nb is continuously precipitated in the cooling process, so that the strength is further improved. V precipitates in a small amount in the hot rolling process, but precipitates in the air cooling process after hot rolling, on one hand, VC is separated out singly or (Nb, V) C is separated out together with Nb to strengthen precipitation, and on the other hand, cementite precipitation is participated in, so as to refine the lamellar spacing of pearlite sheets; the V, nb dissolved in the air-cooled steel also keeps a small amount of precipitation in the stabilizing treatment process after drawing and twisting. The precipitation of Ti and Nb accounts for 95-100% of the total addition, and the precipitation of V accounts for 50-80% of the total addition. The above classified MX-type second phase particles cooperate to provide stress corrosion resistance (i.e., increased tensile strength). The tensile strength of the hot rolled wire rod disclosed by the invention is 1150-1350 MPa, and the area shrinkage rate is more than or equal to 35%.
2. The prestress steel strand disclosed by the invention has good mechanical properties. The hot rolled wire rod disclosed by the invention has excellent tensile property and area shrinkage, so that the mechanical property of the subsequently prepared steel strand is excellent. On the basis of microalloying of V, ti and Nb strong carbide forming elements (namely on the basis of coil characteristics), the stabilizing heat treatment process section in the preparation of the steel strand adopts higher heat treatment temperature and proper heat treatment linear velocity, and cooperates with precipitation of V, ti and Nb nano MX second phases to realize high strength and high plasticity of the steel strand, the tensile strength of the prestressed steel strand is 1860-2060 MPa, and the maximum total elongation is more than or equal to 5.5%.
3. The prestress steel strand disclosed by the invention has good stress corrosion resistance. The tensile strength of the steel strand prepared by the hot rolled wire rod after pickling, drawing, stranding and stabilizing heat treatment can reach 1860-2060 MPa, and the stress corrosion resistance can be satisfied: and carrying out a solution A (analyzing pure ammonium thiocyanate aqueous solution) according to the specification of GB/T21839, and carrying out a stress corrosion test by loading stress with 80% of the actual maximum force, wherein the test group is not less than 5 groups, the minimum value of the stress corrosion breaking time of the prestressed steel is not less than 2 hours, and the median value is not less than 5 hours.
4. The wire rod and the steel strand preparation process disclosed by the invention are relatively mature and suitable for large-scale production. The invention has the advantages that various raw materials and production equipment are common materials/equipment in the market, the process flow is relatively simple, the process condition is easy to realize, the process flow is mature, and the invention is suitable for large-scale production and large-scale popularization.
In the invention, the technical schemes can be mutually combined to realize more preferable combination schemes. Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention may be realized and attained by the structure particularly pointed out in the written description and drawings.
Drawings
The drawings are only for purposes of illustrating particular embodiments and are not to be construed as limiting the invention, like reference numerals being used to refer to like parts throughout the several views.
FIG. 1 is a flow chart of a hot rolled wire preparation method;
FIG. 2 is a photograph of a microstructure of a hot rolled wire rod of example 5.
Detailed Description
Preferred embodiments of the present invention will now be described in detail with reference to the accompanying drawings, which form a part hereof, and together with the description serve to explain the principles of the invention, and are not intended to limit the scope of the invention.
The invention discloses a Mn-Si-V-Ti-Nb-Cr multi-element alloyed hot rolled wire rod, which comprises the following alloy components in percentage by mass: c:0.75 to 0.90 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr: less than or equal to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities.
The action/synergistic action and the content of each component are selected according to the following steps:
c: the steel can effectively improve the tensile strength of the wire rod, and the second phase strengthening elements such as cementite and MX phase are added in the steel, but the excessive C content damages the plasticity. In order to ensure that the tensile strength of the wire rod reaches 1150-1350 MPa, and simultaneously has good plasticity, the area shrinkage is more than or equal to 35 percent, so that the C content is not less than 0.75 percent but not more than 0.90 percent. After Mn, si and Cr are alloyed, hypereutectoid steel is obtained, and through proper air cooling after hot rolling, complete pearlite can be obtained without network cementite. The C content of the steel is 0.75-0.90%.
Mn: the austenite element is stabilized, the eutectoid phase transition temperature and the eutectoid carbon content are reduced, and the influence on the equilibrium phase transition pearlite lamellar spacing is small. The invention mainly utilizes the effect of stabilizing austenite to reduce the temperature of continuous cooling pearlite transformation, thereby refining the lamellar spacing of the pearlite, mn is a main alloy element, and the Mn content is not less than 0.60 percent and not more than 0.90 percent. In addition, mn also plays a deoxidizing role. The invention simultaneously utilizes the deoxidization effect of Mn and the effect of stabilizing austenite. By combining the above, the Mn content of the steel of the invention is 0.6-0.90%.
Si: the steel has excellent relaxation resistance by strongly replacing solid solution strengthening elements, improves the eutectoid phase transition temperature, reduces the eutectoid carbon content, refines the lamellar spacing of pearlite formed below the eutectoid phase transition temperature, has more remarkable strengthening and refining effects as the content is higher, but has more plastic damage when Si is added higher. Thus, the lower Si content is controlled to not more than 0.60%. In addition, si can also play a deoxidizing role, while ultra-low Si control will increase the cost. By combining the above, the Si content of the steel of the invention is 0.10% -0.60%.
Cr: the medium-strength carbide forming element and one of the alloy cementite constituent elements can improve the eutectoid phase transition temperature, reduce the eutectoid carbon content, obviously refine the lamellar spacing of pearlite formed below the eutectoid phase transition temperature, and the higher the Cr content is, the finer the lamellar spacing of the pearlite is, and the higher the strength is. Because Cr is also an alloy element for obviously improving the hardenability, the invention mainly adopts the process strategy of Mn main alloying and hot rolling air cooling to obtain a pearlite structure, so that the strength level of the steel strand reaches 2060MPa, and the upper limit of the Cr content is controlled to be 0.35 percent. The prestressed steel strand with the tensile strength of 1860MPa can be free from adding Cr with the content of less than or equal to 0.10 percent.
V: the strong carbonitride forms elements, the solid solution quantity of the elements in high-carbon steel is much larger than that of Ti and Nb, and the elements can be combined with C to form finer MX-type VC at a lower phase transition temperature, so that the elements play a remarkable role in resisting stress corrosion, and the action mechanism mainly comprises two aspects: on one hand, atoms in the VC lattice are in a shortage position to provide a hydrogen trap, and on the other hand, VC and an iron matrix form a semi-coherent interface to provide the hydrogen trap. In addition, V can also enter cementite to replace part of Fe atoms, namely participate in pearlite transformation, and play a role in refining the lamellar spacing of pearlite. The V content in the steel is controlled to be 0.04-0.10%. In the high-temperature homogenization stage before hot rolling, V may be involved in Ti (C, N) precipitation in a very small amount. Because the hot rolling finishing temperature is higher, V is precipitated in a small amount in the hot rolling stage, VC is separately precipitated or (Nb, V) C is precipitated together with Nb in the air cooling process after hot rolling to strengthen precipitation, cementite precipitation is participated in on the other hand, and the lamellar spacing of pearlite is thinned; the rest V is in solid solution state, and after drawing, a small amount of MX-type second phase particles are continuously precipitated in the stabilizing treatment process due to the dissolution back of C atoms in cementite. The precipitation of V accounts for 50-80% of the total addition. An excessively low V content is detrimental to the stress corrosion resistance of the prestressed steel strands of 1860MPa and above, and the addition of a higher V content (e.g., exceeding 0.10%) increases the alloy cost.
Ti: the strong carbonitride forming element mainly forms TiN or TiC. The solid solution amount of TiN in the steel is small, and the solid solution amount of TiC in the steel is also small. The steel of the invention utilizes TiN to fix N, but in order to avoid the precipitation of TiN in liquid, the lower Ti addition amount is controlled on the basis of controlling the N content to be not more than 0.004%, the atomic ratio of TiN is 3.42, the lower limit of Ti addition is about 3.42 times of the N content and is set to be 0.01%, and the upper limit is not more than 0.025%. Micro Ti after N fixation also precipitates TiC in the hot rolling air cooling process. After pulling, the Ti which is not fully separated out by hot rolling and cooling continues to separate out a small amount of MX type second phase particles in the stabilizing treatment process due to the dissolution back of C atoms in cementite. The precipitation of Ti in the steel accounts for 95-100% of the total addition. The semi-coherent interface formed by TiC and the iron matrix can be a hydrogen trap to play a role in resisting stress corrosion.
Nb: the strong carbonitride forming element, nb combines with N to form NbN with a solid solubility that is an order of magnitude greater than TiN, so Ti in the steel of the present invention fixes N at a high temperature stage, while Nb mainly combines with C to precipitate NbC. Because the content of C in the steel is higher, the solid solubility of NbC is more than 1 order of magnitude less than that of VC, and therefore, the Nb content of the steel is controlled to be 0.01-0.03%. NbC is partially separated out in the hot rolling process, and NbC particles and solid-solution Nb act together to refine austenite grains, so that austenite deformation energy storage is improved, pearlite transformation driving force is improved, and meanwhile, pearlite block masses and lamellar spacing are refined; the incompletely precipitated Nb is continuously precipitated in the cooling process, so that the strength is further improved; after pulling, due to the dissolution back of C atoms in cementite, nb which is insufficiently precipitated by hot rolling and cooling can be continuously precipitated into a small amount of MX-type second phase particles in the stabilizing treatment process. The precipitation of Nb accounts for 95-100% of the total addition, and the stress corrosion resistance is achieved by taking the atomic defect positions in the NbC lattice and the semi-coherent interface of NbC and the iron matrix as hydrogen traps.
Al: the steel of the invention takes the strong deoxidizing element as an optional deoxidizing element, the control content is less than or equal to 0.06 percent, and the excessive Al content easily causes the coarse size of partial inclusion.
P: the toughness and plasticity of the steel are reduced, and the P content of the steel is controlled to be less than or equal to 0.02 percent.
S: the toughness of the steel is reduced, and the S content of the steel is controlled to be less than or equal to 0.005%.
N: an effective interstitial solid solution strengthening element and a second phase strengthening element in the steel. The free N atoms cause the strength of the wire rod to be increased, the toughness to be reduced, and phenomena such as aging and blue embrittlement to be easily caused, so that the total N content and the free N content are as low as possible. Ti is adopted to fix N, so that TiN is formed. In order to avoid the formation of coarse, large amounts of TiN and thus the deterioration of wire rod drawing processability, the total N content needs to be controlled as low as possible. In connection with the experimental or production equipment technical level, the N content of the steel according to the invention does not exceed 0.004%.
Preferably, the alloy components of the hot rolled wire rod are as follows by mass percent: c:0.75 to 0.85 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr: < 0.10%, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities; the hot rolled wire rod with the composition can be used for preparing a prestressed steel strand with the tensile strength of 1860 MPa.
Preferably, the alloy components of the hot rolled wire rod are as follows by mass percent: c:0.75 to 0.85 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr:0.10 to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities; the hot rolled wire rod with the composition can be used for preparing a pre-stressed steel strand with the tensile strength of 1960 MPa.
Preferably, the alloy components of the hot rolled wire rod are as follows by mass percent: c:0.80 to 0.90 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr:0.10 to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities; the hot rolled wire rod with the composition can be used for preparing a prestress steel strand with the tensile strength of 2060 MPa.
Further, the proportion of the microalloy of V, ti and Nb in the hot rolled wire rod is satisfied (V is 0.04 to 0.06 percent, ti is 0.010 to 0.025 percent, nb is 0.01 to 0.03 percent) or (V is 0.07 to 0.10 percent, ti is 0.010 to 0.025 percent, and Nb is less than 0.01 percent). The proportion can better play the strengthening effect of Nb microalloying in the hot rolling process and match with V microalloying, thereby being beneficial to improving the strength and the plasticity of the wire rod/steel strand.
Specifically, the diameter of the hot rolled wire rod is 12.5-14 mm, the microstructure is complete lamellar pearlite, and no network cementite exists.
The diameter of the wire rod for preparing the prestressed steel strand is commonly used to be 12.5-13 mm. The invention makes the hot rolled wire rod obtain refined lamellar pearlite structure with diversified lamellar orientation through special microalloying design and process control, and the hot rolled wire rod with the diameter of 14mm has excellent plasticity, and can be used for preparing prestressed steel wires and steel strands with the same diameter specification as the wire rod with the diameter of 12.5-13 mm, so that excellent mechanical properties can be obtained.
The lamellar pearly-luster structure with refined mass size and lamellar spacing, diversified lamellar orientation has high strength, good deformability and excellent drawing performance. However, if some network cementite is formed, the proeutectoid cementite at these austenite grain boundaries is coarser in size, more brittle, not only is the strength impaired, but also the drawing performance is deteriorated.
Specifically, the tensile strength of the hot rolled wire rod is 1150-1350 MPa, and the area shrinkage is more than or equal to 35%. The hot rolled wire rod has excellent tensile strength and high area shrinkage, and is favorable for preparing the prestressed steel/steel stranded wire with high strength and high toughness.
The invention also discloses a preparation method of the hot rolled wire rod, which comprises the following steps:
s1: batching according to alloy composition, and smelting and casting to obtain a casting blank;
s2: homogenizing the casting blank, namely heating to the austenite homogenizing temperature and preserving heat;
s3: continuously rolling the heat-preserving casting blank after descaling until reaching the target diameter to obtain a semi-finished product wire rod;
s4: and (3) curling and air-cooling the semi-finished wire rod to obtain the finished hot rolled wire rod.
Specifically, in the step S1, excessive raw materials of each alloy element are weighed according to alloy composition, and are added into a high-temperature converter, and casting blanks are formed through converter smelting, LF refining, RH or VD degassing, electromagnetic stirring and continuous casting. The method comprises the steps of controlling relevant parameters of converter smelting, LF refining, RH or VD degassing, carrying out real-time sampling analysis on molten steel in the converter, pouring out the molten steel when each element component reaches a preset value/range, and carrying out electromagnetic stirring and continuous casting. The process and the parameters are controlled to be a mature alloy preparation process in the prior art, and the parameters can be adjusted in the implementation process according to practical experience and specific alloy composition.
Specifically, the austenite homogenization temperature in the step S2 is 1180-1250 ℃, and the heat preservation time is 0.5-3 h. When the homogenization temperature is too high, the TiN part in the casting blank can be completely dissolved in a solid state, so that austenite grains are coarsened, and the energy cost is increased; too low homogenization may result in insufficient solid solution of strong carbonitride forming elements such as Nb, V, etc. in the steel, thereby affecting the subsequent finished product properties. The homogenization heat preservation time is too long, austenite grains coarsen, the energy cost is increased, and the production efficiency is not facilitated; the homogenization heat preservation is too short, and the thickness and temperature uniformity of the casting blank are difficult to ensure. Therefore, the heat preservation time is controlled to be 0.5-3 h.
Preferably, when the Nb content in the alloy is 0.01% -0.03%, the austenite homogenization temperature is 1200-1250 ℃, so that more than 80% of Nb is in a solid solution state.
Illustratively, the descaling operation in step S3 may employ a high-pressure water descaling technique or other conventional descaling process. The descaling operation has the function of removing the iron scales so as to prevent the iron scales from being pressed into the surface of the alloy/wire rod to generate defects, thereby improving the surface quality of the product.
Specifically, the heating temperature before hot rolling in the step S3 is 1180-1250 ℃ (namely the austenite homogenizing temperature in the step S2), the hot rolling is directly carried out after heat preservation, and the hot rolling finishing temperature is 890-950 ℃. The final rolling temperature is too high, the hot-rolled austenite grains are coarser, and the effect of refining the hot-rolled austenite grains by Nb microalloying is not obvious; too low a finish rolling temperature will result in more V precipitation and a significant increase in rolling force.
Specifically, the air cooling speed after the hot rolling in the step S4 and before the hot rolling reaches 500 ℃ is 1.5 ℃/S-3.5 ℃/S. The air cooling speed is more than or equal to 1.5 ℃/s, and the formation of proeutectoid cementite (network cementite) can be avoided; when the air cooling speed is more than or equal to 3.5 ℃, a large amount of bainite tissues can be formed, and even part of superhard martensite tissues are formed in the subsequent cooling process, so that the drawing is not facilitated, and the excessive air cooling speed is avoided.
The invention also discloses a prestress steel strand, which is prepared from the hot rolled wire rod or the hot rolled wire rod prepared by the preparation method through pickling, cold drawing, stranding and stabilizing heat treatment.
Illustratively, the pickling may employ the following operations: the wire rods are unpacked and loosened and then immersed in pickling solution, the pickling solution can be 10% -15% hydrochloric acid, pickling is carried out for about 30 minutes at normal temperature, the wire rods are lifted to a suspended bracket above a pickling tank after pickling is finished, and the wire rods shake in a small range, so that the pickling solution carried out by the wire rods flows back into the tank.
By way of example, cold drawing, namely selecting a wire drawing die/die hole with proper aperture at room temperature, so that the wire rod passes through the die hole under the action of strong external force, and the wire rod is subjected to plastic deformation, thereby obtaining the steel wire with corresponding size.
The stranding is to wind a plurality of steel wires once to manufacture a steel strand, and a mechanical stranding machine can be adopted for stranding, wherein the number of the steel wires in the steel strand is not less than 3.
Specifically, the diameter of the drawn monofilament is 5mm in the cold drawing process, the temperature of the stabilizing heat treatment after stranding is 400-460 ℃, and the linear speed is 1.2-2.0 m/s. The stabilizing heat treatment process is fully separated out and matched with the V, ti and Nb microalloy, the temperature is matched with the linear velocity, the linear velocity is high when the temperature is high, the linear velocity is low when the temperature is low, and the V, ti and Nb nano MX second phase particle separation is facilitated, and the strong plasticity is improved.
Specifically, the tensile strength of the prestressed steel strand is 1860-2060 MPa, the total elongation of the maximum force is more than or equal to 5.5%, and the stress corrosion resistance meets the following conditions: and carrying out a solution A (analyzing pure ammonium thiocyanate aqueous solution) according to the specification of GB/T21839, and carrying out a stress corrosion test by loading stress with 80% of the actual maximum force, wherein the test group is not less than 5 groups, the minimum value of the stress corrosion breaking time of the prestressed steel is not less than 2 hours, and the median value is not less than 5 hours. Solution a (analytically pure aqueous ammonium thiocyanate) was: 200g NH 4 SCN was dissolved in 800mL of distilled or demineralised water to make an ammonium thiocyanate solution. Ammonium thiocyanate is analytically pure, where NH 4 SCN content of at least 98.5%, cl - ＜0.005％,S 2- ＜0.001％。
The advantages of the invention in terms of precise control of the composition and process parameters of the wire rod/strand will be demonstrated in the following specific examples and comparative examples. The chemical composition of the steels of examples 1 to 8 and comparative examples 1 to 5 are shown in Table 1, the specific rolling and cooling process parameters are shown in Table 2, and the mechanical properties are shown in Table 3.
Examples 1-6 were smelted in a converter, LF refined, RH degassed, electromagnetic stirred, continuous cast to 160mm thick by 160mm wide square billets, cut to 12000mm long billets, rolled to 1180-1250 ℃, kept at temperature for 0.5-3 h, hot rolled to 12.5-14 mm diameter wire rods after tapping, and final rolling temperature 890-950 ℃. The air cooling speed is 1.5-3.5 ℃/s before cooling to 500 ℃ after hot rolling.
Examples 7 to 8 were smelted by a converter, LF refined, VD degassed, electromagnetic stirred, continuous cast into square billets 160mm (thick) ×160mm (wide), cut into billets 12000mm long, rolled and heated to 1200-1250 ℃, respectively kept for 1-2 hours, hot rolled into wire rods 13mm in diameter after tapping, and cooled to 1.8-2.7 ℃/s before hot rolling at 900-930 ℃.
The preparation methods of comparative examples 1 to 5 are substantially the same as those of example 1, and specific formulations or process parameter differences are shown in tables 1 and 2.
Table 1 chemical composition wt% of examples and comparative examples
| Numbering device | C | Mn | Si | Cr | V | Ti | Nb | Al | P | S | N |
| Example 1 | 0.75 | 0.69 | 0.36 | 0.06 | 0.05 | 0.013 | 0.026 | 0.023 | 0.012 | 0.0044 | 0.0038 |
| Example 2 | 0.83 | 0.68 | 0.22 | 0.02 | 0.08 | 0.016 | 0.004 | 0.015 | 0.011 | 0.0028 | 0.0029 |
| Example 3 | 0.78 | 0.87 | 0.42 | 0.11 | 0.09 | 0.022 | 0.005 | 0.013 | 0.014 | 0.0034 | 0.0037 |
| Example 4 | 0.80 | 0.76 | 0.46 | 0.18 | 0.04 | 0.018 | 0.028 | 0.011 | 0.013 | 0.0029 | 0.0036 |
| Example 5 | 0.81 | 0.88 | 0.58 | 0.12 | 0.06 | 0.017 | 0.012 | 0.008 | 0.012 | 0.0020 | 0.0035 |
| Example 6 | 0.86 | 0.77 | 0.46 | 0.34 | 0.08 | 0.011 | 0.003 | 0.016 | 0.014 | 0.0041 | 0.0031 |
| Example 7 | 0.84 | 0.62 | 0.37 | 0.27 | 0.05 | 0.023 | 0.018 | 0.007 | 0.013 | 0.0048 | 0.0023 |
| Example 8 | 0.90 | 0.79 | 0.45 | 0.26 | 0.10 | 0.025 | 0.004 | 0.015 | 0.011 | 0.0037 | 0.0036 |
| Comparative example 1 | 0.81 | 0.74 | 0.48 | 0.19 | 0.004 | 0.007 | 0.004 | 0.022 | 0.013 | 0.0048 | 0.0044 |
| Comparative example 2 | 0.83 | 0.84 | 0.22 | 0.03 | 0.02 | 0.004 | 0.003 | 0.005 | 0.012 | 0.0043 | 0.0038 |
| Comparative example 3 | 0.85 | 0.63 | 0.28 | 0.16 | 0.006 | 0.005 | 0.005 | 0.013 | 0.014 | 0.0036 | 0.0033 |
| Comparative example 4 | 0.80 | 0.77 | 0.12 | 0.12 | 0.03 | 0.006 | 0.004 | 0.011 | 0.014 | 0.0038 | 0.0037 |
| Comparative example 5 | 0.80 | 0.65 | 0.11 | 0.04 | 0.003 | 0.003 | 0.003 | 0.007 | 0.013 | 0.0048 | 0.0040 |
Table 2 specific hot rolling cooling process parameters of examples and comparative examples
Table 3 diameter specification and mechanical properties of examples and comparative examples
| Numbering device | Diameter/mm | Tensile strength MPa | Area reduction/% |
| Example 1 | 14 | 1170 | 41.0 |
| Example 2 | 13 | 1220 | 39.0 |
| Example 3 | 13 | 1295 | 39.5 |
| Example 4 | 12.5 | 1310 | 38.5 |
| Example 5 | 13 | 1355 | 38.5 |
| Example 6 | 13 | 1380 | 37.0 |
| Example 7 | 14 | 1270 | 39.0 |
| Example 8 | 12.5 | 1385 | 35.5 |
| Comparative example 1 | 13 | 1210 | 35.0 |
| Comparative example 2 | 13 | 1225 | 34.0 |
| Comparative example 3 | 14 | 1190 | 34.0 |
| Comparative example 4 | 12.5 | 1230 | 33.0 |
| Comparative example 5 | 13 | 1135 | 36.5 |
As can be seen from tables 2 and 3, the tensile strength of the hot rolled wire rods of examples 1 to 8 is 1150MPa to 1350MPa (e.g., 1170 to 1385 MPa), the reduction of area is not less than 35% (e.g., 35.5 to 41.0%), and the diameter gauge is 12.5 to 14mm.
And the tensile strength level of the coil rod with the hot rolled diameter of 12.5-14 mm in comparative examples 1-5 is 1130-1230 MPa, and the area shrinkage is 33.0-36.5%. The plasticity of comparative examples 1 to 5 is relatively low compared to examples 1, 2, 3 and 7 of similar strength.
Overall, the overall performance of examples 1-8 is significantly better than the comparative example, with higher tensile strength and higher reduction of area.
Table 4 example wire rod corresponding prestressed steel stabilization heat treatment process and performance
As shown in Table 4, the high-strength wire rods of examples 1 to 8 are subjected to acid washing and drawing to form steel wires (5.05 to 5.25 mm) with the diameter of 5mm and are subjected to stabilization heat treatment after stranding (7-wire steel strand), the tensile strength of the prestressed steel strand reaches 1860 to 2060MPa, and the stress corrosion resistance meets the following conditions: and carrying out a solution A (analyzing pure ammonium thiocyanate aqueous solution) according to the specification of GB/T21839, and carrying out a stress corrosion test by loading stress with 80% of the actual maximum force, wherein the test group is not less than 5 groups, the minimum value of the stress corrosion breaking time of the prestressed steel is not less than 2 hours, and the median value is not less than 5 hours. The high-strength wire rods of comparative examples 1 to 5 are subjected to acid washing and drawing to obtain steel wires with diameters of 5mm (5.05 to 5.25 mm), and after stranding, the steel wires are subjected to stabilization heat treatment, the tensile strength of the prestressed steel strands is 1860MPa, the minimum stress corrosion breaking time is more than or equal to 2 hours, but the median value is only 2.8 to 4.1 hours, and the requirement of more than or equal to 5 hours is not met.
The present invention is not limited to the above-mentioned embodiments, and any changes or substitutions that can be easily understood by those skilled in the art within the technical scope of the present invention are intended to be included in the scope of the present invention.
Claims (10)
1. A Mn-Si-V-Ti-Nb-Cr multi-element alloyed hot rolled wire rod is characterized in that: the alloy components of the hot rolled wire rod are as follows by mass percent: c:0.75 to 0.90 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr: less than or equal to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities.
2. The hot rolled wire rod as claimed in claim 1, wherein: the alloy components of the hot rolled wire rod are as follows by mass percent: c:0.80 to 0.90 percent, mn:0.60% -0.90%, si:0.10 to 0.60 percent, cr:0.10 to 0.35 percent, V:0.04 to 0.10 percent of Ti:0.010% -0.025%, nb: less than or equal to 0.03 percent, al: less than or equal to 0.06 percent, P: less than or equal to 0.02 percent, S: less than or equal to 0.005 percent, N: less than or equal to 0.004 percent, and the balance of Fe and unavoidable impurities.
3. The hot rolled wire rod as claimed in claim 1, wherein: the ratio of the V, ti and Nb microalloy in the hot rolled wire rod is as follows: 0.04 to 0.06 percent of Ti:0.010% -0.025%, nb:0.01% -0.03%, or V:0.07 to 0.10 percent of Ti:0.010% -0.025%, nb: less than 0.01%.
4. The hot rolled wire rod as claimed in claim 1, wherein: the diameter of the hot rolled wire rod is 12.5-14 mm, the microstructure is complete lamellar pearlite, and no network cementite exists.
5. The hot rolled wire rod as claimed in claim 1, wherein: the tensile strength of the hot rolled wire rod is 1150-1350 MPa, and the area shrinkage rate is more than or equal to 35%.
6. A method for producing a hot rolled wire rod according to any one of claims 1 to 5, comprising the steps of:
s1: batching according to alloy composition, and smelting and casting to obtain a casting blank;
s2: homogenizing the casting blank, namely heating to the austenite homogenizing temperature and preserving heat;
s3: continuously rolling the heat-preserving casting blank after descaling until reaching the target diameter to obtain a semi-finished product wire rod;
s4: and (3) curling and air-cooling the semi-finished wire rod to obtain the finished hot rolled wire rod.
7. The method of manufacturing according to claim 6, wherein: the austenite homogenizing temperature in the step S2 is 1180-1250 ℃, and the heat preservation time is 0.5-3 h.
8. The method of manufacturing according to claim 6, wherein: when the Nb content in the alloy is 0.01% -0.03%, the austenite homogenizing temperature is 1200-1250 ℃.
9. The method of manufacturing according to claim 6, wherein: and S4, the air cooling speed after hot rolling and before finishing rolling to 500 ℃ is 1.5 ℃/S-3.5 ℃/S.
10. The utility model provides a prestressing force steel strand wires which characterized in that: the steel strand is manufactured by acid washing, cold drawing, stranding and stabilizing heat treatment of the hot rolled wire rod according to any one of claims 1 to 5 or the hot rolled wire rod manufactured by the manufacturing method according to any one of claims 6 to 9.
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20000025694A (en) * | 1998-10-13 | 2000-05-06 | 이구택 | High strength steel for wire rod and method for manufacturing wire rod using the same |
| US20090087336A1 (en) * | 2006-06-01 | 2009-04-02 | Seiki Nishida | High-carbon steel wire rod of high ductility |
| CN108138285A (en) * | 2015-10-23 | 2018-06-08 | 新日铁住金株式会社 | Wire Drawing steel wire material |
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20000025694A (en) * | 1998-10-13 | 2000-05-06 | 이구택 | High strength steel for wire rod and method for manufacturing wire rod using the same |
| US20090087336A1 (en) * | 2006-06-01 | 2009-04-02 | Seiki Nishida | High-carbon steel wire rod of high ductility |
| CN108138285A (en) * | 2015-10-23 | 2018-06-08 | 新日铁住金株式会社 | Wire Drawing steel wire material |
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