CN105154788A - Heat-resistant alloy steel component having trans-scale multiphase in-situ enhancement effect and microstructure control process thereof - Google Patents
Heat-resistant alloy steel component having trans-scale multiphase in-situ enhancement effect and microstructure control process thereof Download PDFInfo
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Abstract
The invention discloses a heat-resistant alloy steel component having trans-scale multiphase in-situ enhancement effect and a microstructure control process thereof. The component is characterized by comprising the following alloy elements in percentage by mass: 0.20-0.45% of C, 1.0-2.0% of Mn, 2.0-4.0% of Cr, 1.5-3.0% of Ni, 0.3-0.8% of Ti, 0.01-0.1% of Mo, 0.2-0.8% of Cu, 0.005-0.015% of N, 0.001-0.008% of RE, P not more than 0.005%, 0.005-0.01% of S, and one or two of V and Nb. The heat-resistant alloy steel component having trans-scale multiphase in-situ enhancement effect and the microstructure control process thereof, provided by the invention, can prominently improve the toughness, the wear resistance, the high-temperature structure stability and the mechanical performance of alloy steel; and the method is simple, and is easy to be realized.
Description
Technical field
The present invention relates to a kind of tool across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick and microstructure modulation process thereof, particularly relate to a kind of at a high speed, the refractory alloy composition of steel of being on active service under the extreme harsh working condition such as heavy duty and high temperature and microstructure modulation process thereof, belong to new metallic substance thermomechanical treatment process technical field.
Background technology
Along with the development of science and technology, mechanized equipment is gradually towards future developments such as high speed, heavy duties, and its design and operation condition is day by day harsh, has higher requirement to over-all propertieies such as its physics, chemistry and mechanics.Low-carbon (LC) (nitrogen) steel alloy, because of wear-resisting, anti-corrosion, the antifatigue of its excellence and the characteristic such as obdurability and good heat accumulation, thermal conduction and heat exchange, has broad application prospects improving in mechanical key component military service efficiency and safe reliability.Its core technology, except the optimization design of steel alloy system, concise metallurgical technology, is also the optimal control of steel alloy microtexture and structure.
The element such as Ti, Nb, V and Mo adding trace in steel can not only refine austenite and ferrite crystal grain, and a large amount of nanometer precipitated phases can also be formed at the fault location such as crystal boundary, dislocation, under the condition not damaging steel plasticity and toughness, the intensity of steel can be improved significantly.Therefore, the focus direction that the effect of microalloy element in crystal grain thinning and precipitation strength has become the research of high-performance low-carbon micro-alloyed steel how is given full play to.
At present, the control technique of precipitated phase has become study hotspot both domestic and external, the equally distributed tissue with nanometer MX (<50nm) carbonitride of low alligatoring speed on lath inside, lath circle, lath bundle circle, crystalline region circle and original austenite crystal prevention is obtained by alloying constituent and heat treatment process technical optimization, the pinning effect of such precipitated phase to dislocation and interface can strengthen matrix, and MX is on good terms and accesses the creep rupture strength of obviously lifting steel.Mainly through Orowan mechanism, these precipitated phases are walked around for large-size precipitated phase dislocation; the precipitated phase (M3C, M23C6, M7C3 etc.) of 100-200nm adds dislocation and walks around area; the position dislocation wall of subgrain or born of the same parents' shape substructure in creep process being formed and destroy is balanced; maintain the high-temperature stability of subgrain, thus improve material at high temperature stability.JFE Iron And Steel Company of Japan adopts 0.04%C-1.5%Mn-0.09%Ti-0.2%Mo component system, precipitation strength mode is utilized successfully to develop 1180MPa level automobile sheetsteel band steel, the feature of this kind of steel is the alternate precipitation (Ti single ferrite matrix being dispersed with the about 3nm that takes measurements greatly, Mo) C, there is no the phase boundary of soft or hard phase, there is high strength and high hole expansibility.The people such as Sun Yi have studied Nb-Ti microalloy pick-up behavior in steel in controlled cooling model mode production process, result shows, interval by the quick Precipitation Temperature avoiding 900-950 DEG C of carbonitride, and suitably increase the volume fraction that speed of cooling effectively can improve the Carbide Precipitation particle of below 20nm, remarkable refinement precipitation size, thus improve precipitation strength to the contribution of yield strength.The people such as Wang Zemin have studied the impact of Mo on Carbide Precipitation in Nb-Mo-V microalloyed steel, research shows, in drawing process, Mo segregation inhibits Nb, V to diffuse to carbide from ferrite at carbide skin, and reduce the speed that in matrix, C and alloying element spread to carbide, effectively inhibit growing up of carbide particle.Publication number be CN101906590A patent document discloses a kind of austenitic heat-resistance steel and the manufacture method thereof with strengthened nano precipitated phase, its manufacture method is: the raw material of constitution element is made steel part through melting, hot-work and cold working, then carries out finished heat treatment.Finished heat treatment is in two steps: the first step, and solution treatment, is heated to 1170-1250 DEG C by steel part, keeps 30-60min, is then cooled to room temperature; Second step, anneal, is heated to 800-950 DEG C by the steel part after solution treatment, and keep 30-240min, then air cooling is to room temperature.This invention guarantees that steel is evenly distributed with highdensity NbCrN type nano-strengthening phase at intra-die, size is between 20-60nm, in every micron square area, nano-strengthening phase granule number is at 5-30, the M23C6 type carbide that crystal boundary distributes accounts for the percentage ratio of grain boundary area lower than 20%, creep rupture strength significantly improves, and resistance to high temperature corrosion performance might as well.Can find out, this complex technical process, carboritride kind in product, size are single, its comprehensive mechanical property especially high temperature microstructure and mechanical property be difficult to meet at a high speed, performance requirement under the harsh operating mode such as heavy duty and high temperature.The present invention is combined with modifier treatment by compound thermomechanical treatment, and utilize in-situ authigenic ultra tiny composite carbon nitride principle, Reasonable Regulation And Control carboritride precipitate size and distribution, improve materials microstructure, promotes high temperature microstructure and stable mechanical property.
Summary of the invention
Technical problem to be solved by this invention is, provides a kind of refractory alloy composition of steel of tool across the heterogeneous In-sltu reinforcement effect of yardstick of obdurability, wear resistance, high temperature microstructure stability and the mechanical property that significantly can improve steel alloy; Further, the invention provides a kind of method simple, be easy to realize, the wild phase obtained is original position phase-change product, be distributed between disperse phase on ferrite matrix, yardstick is nanometer to the tool across yardstick compound of submicron across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick.
For solving the problems of the technologies described above, the technical solution used in the present invention is:
Tool is across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: the alloying element comprising following mass percent wt%: C:0.20 ~ 0.45, Mn:1.0 ~ 2.0, Cr:2.0 ~ 4.0, Ni:1.5 ~ 3.0, Ti:0.3 ~ 0.8, Mo:0.01 ~ 0.1, Cu:0.2 ~ 0.8, N:0.005 ~ 0.015, RE:0.001 ~ 0.008, P :≤0.005, S:0.005 ~ 0.01; Also comprise any one or two kinds in V, Nb, V and Nb content summation is 0.05 ~ 0.3; Surplus is Fe and inevitable impurity.
The mass percent of V and Nb is respectively V:0.02 ~ 0.15wt%, Nb:0.01 ~ 0.15wt%.
Aforesaid alloying element forms heat-resisting alloy steel through refining rolling.
Tool, across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: comprise the following steps:
S1, heat-resisting alloy steel examination is heated to 1100 ~ 1200 DEG C and makes its austenitizing, except the carbon of Ti, nitride, all the other alloying elements are solid-solution in austenite completely, then High Temperature Pre distortion is carried out in air cooling to 950 ~ 1050 DEG C, deflection is 15% ~ 35%, rate of deformation is 0.1/s ~ 0.8/s, forms the deformed austeaite tissue that the carbide of Ti, Nb, nitride or carbonitride strengthen after High Temperature Pre distortion;
S2, air cooling to 850 ~ 900 DEG C are organized to carry out multi-pass deformation the deformed austeaite in S1, the timed interval controlling each passage is 80 ~ 900s and adds in time to vulcanize temperature, distortion total amount is 20% ~ 60%, rate of deformation is 0.2/s ~ 1/s, form the deformation ferritic structure of the carbide of Ti, Nb, V, nitride or carbonitride dispersion-strengthened after multi-pass deformation, and air cooling is to room temperature;
S3, carry out modifier treatment to the deformation ferritic structure in S2, quenching temperature is 870 ~ 890 DEG C, and soaking time is 0.5 ~ 2 hour, and water-cooled is to room temperature; Tempering temperature is 550 ~ 650 DEG C, and tempering time is 1 ~ 4h, and air cooling is to room temperature.
Described deformed austeaite tissue and deformation ferritic structure are original position phase-change product, are distributed on ferrite matrix between disperse phase, yardstick be nanometer to submicron across yardstick compound; Nanoscale wild phase comprises the multiple combination of MX type carbon, nitride, and it is of a size of 3 ~ 50nm; Submicron-scale wild phase comprises the combination of Me3C, Me23C6, Me7C3, Me2C and MeC type carboritride, and it is of a size of 100 ~ 300nm; M represents metal element Ti in alloying element, Nb, V and Mo, and X represents carbon or nitrogen element, and C represents carbon, and Me represents metallic element Fe, Cr, Mo in alloying element.
The multiple combination of described MX type carbon, nitride comprises TiN, TiC, NbC, NbN, Ti (C, N), Nb (C, N), VN, VC, V (C, N), (Ti, Mo) C, (Ti, Mo) N or (Ti, Mo) (C, N).
The number of times of described multi-pass deformation is at least 3 times.
The deformation of described deformed austeaite tissue and deformation ferritic structure is all carried out on intelligent control swaging rolling plant, and heating, conveying, distortion and experimental parameter are all realized by Controlling System.
Described heating is all adopt induction heating mode, and the heating efficiency of induction heating mode is high, temperature control accurate, test specimen is oxidized and deformation extent is little.
Technique comprises three processes: low-carbon alloy steel curved beam is heated to 1100 ~ 1200 DEG C and makes its complete austenitizing by (1), other alloying element except the carbon of Ti, nitride is fully solid-solution in austenite, carry out High Temperature Pre deformation process subsequently, carbon, the nitride of induction Ti, Nb are separated out, inhibiting grain growth, for other alloy carbon, nitride and ferritic precipitation provide phase driving force and thermodynamics and dynamics condition; (2) at a lower temperature multi-pass deformation is carried out to High Temperature Pre distortion sample, obtain the microstructure of a large amount of tiny alloy carbon of Dispersed precipitate, nitride on ferrite matrix; (3) carry out modifier treatment to the sample after compound thermomechanical treatment, eliminate structural stress, proeutectoid ferrite also even thinning microstructure, original position forms the microstructure of nanometer and the enhancing of submicron compound yardstick carbonitride.This technique is simple, be easy to realize, and significantly can improve the obdurability of steel alloy, wear resistance, high temperature microstructure stability and mechanical property.
The principle of the invention is as follows:
For heat-resisting alloy steel, the kind of alloy carbon, nitride, size, pattern, structure and distribution are one of key factors determining its comprehensive mechanical property.The present invention is dissolved it by thermomechanical treatment and normative heat treatment parameter, precipitate and pick-up behavior carries out adjustment control.When heating raw materials to 1100 ~ 1200 DEG C, the too high fast growth easily causing austenite crystal of Yin Wendu.The feature of the carbon of Ti, nitride Precipitation Temperature very high (1000 ~ 1429 DEG C) and size more tiny (2 ~ 10nm) is utilized in the present invention, it can be used as the high temperature precipitated phase of stable existence, and the feature higher according to its diffusion activation energy, by the optimal control of soaking time, the long-range meeting Ti diffuses to form carbon, the nitride of tiny Ti, to stop growing up of austenite crystal.
Phase transformation when heat-resisting alloy steel after austenitizing cools mainly controls by THERMODYNAMICAL STUDY and dynamic conditions.Increase stored energy and transformation temperature improve the major measure of phase driving force, but the two is interactional.Larger stored energy and be conducive to carrying out and the structure refinement of phase in version compared with low transformation temperature.But, when transformation temperature is too low, although be conducive to the increase of accumulation deformation effect, be unfavorable for carrying out smoothly of viscous deformation, cause material or product defects rate or condemnation factor high.Therefore, the present invention adopts the mode of compound thermomechanical treatment to realize the regulation and control to refractory alloy structure of steel.First, High Temperature Pre distortion is carried out to austenite, and by the control of texturing temperature and rate of deformation, increase dislocation desity and intracrystalline, grain boundary defects in austenite, be aided with the carbon of Ti, Nb, nitride to the pinning effect of dislocation simultaneously, stop its dynamically, static recovery and recrystallize, improve stored energy.Then, reduce temperature carry out multi-pass deformation and vulcanize gentle passage deformation rate and the control in the timed interval by adding, improve stored energy on the one hand, promote that the ferritic precipitation of deformation also suppresses its Recovery and recrystallization, make the alloy carbon such as V, Mo, nitride has enough energy and time fully to separate out and keep less grain-size (3 ~ 50nm).On the other hand, because the alloy carbon such as Ti, Nb, V, Mo, nitride are usually located at intracrystalline subgrain boundary, dislocation and distortion band place, heterogeneous forming core core can be provided for Intragranular Acicular Ferrite, simultaneously the coherency of alloy carbon, some crystal face of nitride and the low index crystal plane of ferrite such as Ti, Nb, V, Mo is high, make ferrite that its direct extension can be relied on to grow up, promote the heterogeneous nucleation of Intragranular Acicular Ferrite, improve phase in version efficiency, and refining grain size.Finally, by modifier treatment, the refractory alloy structure of steel after compound thermomechanical treatment is adjusted.By the control of the experimental parameters such as quenching, tempering temperature, the type of cooling, eliminate structural stress further, improve tissue size and homogeneity.Due to Ti, Nb, the carbon of V, nitride solvent temperature is higher, thus can be remained wholly or in part when austenitizing, inhibiting grain growth also becomes the core of phase deformed nucleus, Cr is promoted in quench cooled and drawing process, Mo, the Heterogeneous Nucleation of the element such as Ni and rare earth, form micron order Fe, the carboritride of Mo and Cr (is mainly Me3C, Me2C, MeC, Me23C6, Me7C3 etc.), the nanoscale Ti of a large amount of Dispersed precipitate, Nb, the precipitate of V, a large amount of micron order Mo, carbide and the rare earth compound of Cr distribute alternately, be conducive to thinning microstructure, strengthening matrix, improve its obdurability and mechanical behavior under high temperature and structure stability.
The invention has the beneficial effects as follows:
Tool is across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, and the method is simple, be easy to realize.The wild phase obtained is original position phase-change product, is distributed on ferrite matrix between disperse phase, yardstick be nanometer to submicron across yardstick compound; Nanoscale wild phase is TiN, TiC, NbC, NbN, Ti (C, N), Nb (C, N), VN, VC, V (C, N), (Ti, Mo) C, (Ti, Mo) N or (Ti, Mo) (C, the multiple combination of MX type carbon, nitride such as N), it is of a size of 3 ~ 50nm; Submicron-scale wild phase is the combination of Me3C, Me23C6, Me7C3, Me2C and MeC type carboritrides such as Fe, Cr, Mo, and it is of a size of 100 ~ 300nm.This structure can make steel alloy have excellent intensity and toughness, has good high temperature microstructure stability and wear resistance simultaneously, to meet material or the component long lifetime at high temperature, at a high speed, under the harsh operating mode such as high loading, high-level efficiency user demand.
Accompanying drawing explanation
Fig. 1 is micro-organization chart of the present invention.
Embodiment
Below in conjunction with accompanying drawing, the present invention is further described.
Embodiment 1:
Tool, across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: the alloying element comprising mass percent wt% as described in Table 1:
The chemical composition of table 1 test steel alloy:
Tool is as follows across the microstructure modulation process of the heat-resisting alloy steel of yardstick heterogeneous In-sltu reinforcement effect:
(1) above-mentioned forging stock material is incubated 0.5h through induction heating to 1150 DEG C, then carry out flat-die forging distortion at 1000 DEG C, deformation quantity is 20%, rate of deformation is 0.6/s, controls air cooling to 880 DEG C;
(2) carry out 3 passage distortion at 880 DEG C to sample, add and vulcanize temperature and the interval time controlled between passage is 120s, total deflection is 35%, controls air cooling to room temperature;
(3) sample after thermomechanical treatment is heated to 890 DEG C of austenitizings, soaking time is 0.5h, then quenches, and quenchant is water, and after air cooling to room temperature, rear sample is heated to 650 DEG C of tempering, and tempering time is 2h.
Embodiment 2:
Tool, across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: the alloying element comprising mass percent wt% as described in Table 1.
Tool is as follows across the microstructure modulation process of the heat-resisting alloy steel of yardstick heterogeneous In-sltu reinforcement effect:
(1) above-mentioned forging stock material is incubated 1h through induction heating to 1100 DEG C, then carry out flat-die forging distortion at 950 DEG C, deformation quantity is 15%, rate of deformation is 0.2/s, controls air cooling to 850 DEG C;
(2) carry out 2 passage distortion at 850 DEG C to sample, add and vulcanize temperature and the interval time controlled between passage is 90s, total deflection is 25%, controls air cooling to room temperature;
(3) sample after thermomechanical treatment is heated to 870 DEG C of austenitizings, soaking time is 2h, then quenches, and quenchant is water, and after air cooling to room temperature, rear sample is heated to 550 DEG C of tempering, and tempering time is 4h.
Embodiment 3:
Tool, across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: the alloying element comprising mass percent wt% as described in Table 1.
Tool is as follows across the microstructure modulation process of the heat-resisting alloy steel of yardstick heterogeneous In-sltu reinforcement effect:
(1) above-mentioned forging stock material is incubated 20min through induction heating to 1200 DEG C, then carry out flat-die forging distortion at 1050 DEG C, deformation quantity is 35%, rate of deformation is 0.8/s, controls air cooling to 900 DEG C;
(2) carry out 5 passage distortion at 900 DEG C to sample, add and vulcanize temperature and the interval time controlled between passage is 300s, total deflection is 60%, controls air cooling to room temperature;
(3) sample after thermomechanical treatment is heated to 880 DEG C of austenitizings, soaking time is 1h, then quenches, and quenchant is water, and after air cooling to room temperature, rear sample is heated to 600 DEG C of tempering, and tempering time is 2h.
Embodiment 4:
Tool, across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: the alloying element comprising mass percent wt% as described in Table 1.
Tool is as follows across the microstructure modulation process of the heat-resisting alloy steel of yardstick heterogeneous In-sltu reinforcement effect:
(1) above-mentioned forging stock material is incubated 1h through induction heating to 1100 DEG C, then carry out flat-die forging distortion at 1000 DEG C, deformation quantity is 30%, rate of deformation is 0.6/s, controls air cooling to 870 DEG C;
(2) carry out 4 passage distortion at 870 DEG C to sample, add and vulcanize temperature and the interval time controlled between passage is 180s, total deflection is 40%, controls air cooling to room temperature;
(3) sample after thermomechanical treatment is heated to 890 DEG C of austenitizings, soaking time is 1h, then quenches, and quenchant is water, and after air cooling to room temperature, rear sample is heated to 620 DEG C of tempering, and tempering time is 1.5h.
As shown in Figure 1, be the micro-organization chart of sample after the present embodiment compound thermomechanical treatment process.
As shown in Figure 1, the ferrite of separating out along original austenite crystal prevention through compound thermomechanical treatment is elongated, fragmentation, the ferrite crystal grain that major part is elongated forms the shaft-like ferrites such as tiny after dynamic recrystallization, and grain refining, crystal boundary increase the precipitation facilitating carboritride.
Embodiment 5:
Tool, across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: the alloying element comprising mass percent wt% as described in Table 2.
The chemical composition of table 2 test steel alloy:
Tool is as follows across the microstructure modulation process of the heat-resisting alloy steel of yardstick heterogeneous In-sltu reinforcement effect:
S1, heat-resisting alloy steel examination is heated to 1100 DEG C and makes its austenitizing, except the carbon of Ti, nitride, all the other alloying elements are solid-solution in austenite completely, then air cooling to 950 DEG C carries out High Temperature Pre distortion, deflection is 15%, rate of deformation is 0.1/s, forms the deformed austeaite tissue that the carbide of Ti, Nb, nitride or carbonitride strengthen after High Temperature Pre distortion;
S2, air cooling to 850 DEG C is organized to carry out multi-pass deformation the deformed austeaite in S1, the timed interval controlling each passage is 80s and adds in time to vulcanize temperature, distortion total amount is 20%, rate of deformation is 0.2/s, form the deformation ferritic structure of the carbide of Ti, Nb, V, nitride or carbonitride dispersion-strengthened after multi-pass deformation, and air cooling is to room temperature;
S3, carry out modifier treatment to the deformation ferritic structure in S2, quenching temperature is 870 DEG C, and soaking time is 0.5 hour, and water-cooled is to room temperature; Tempering temperature is 550 DEG C, and tempering time is 1h, and air cooling is to room temperature.
Described deformed austeaite tissue and deformation ferritic structure are original position phase-change product, are distributed on ferrite matrix between disperse phase, yardstick be nanometer to submicron across yardstick compound; Nanoscale wild phase comprises the multiple combination of MX type carbon, nitride, and it is of a size of 3nm; Submicron-scale wild phase comprises the combination of Me3C, Me23C6, Me7C3, Me2C and MeC type carboritride, and it is of a size of 100nm; M represents metal element Ti in alloying element, Nb, V and Mo, and X represents carbon or nitrogen element, and C represents carbon, and Me represents metallic element Fe, Cr, Mo in alloying element.
The multiple combination of described MX type carbon, nitride comprises TiN, TiC, NbC, NbN, Ti (C, N), Nb (C, N), VN, VC, V (C, N), (Ti, Mo) C, (Ti, Mo) N or (Ti, Mo) (C, N).
The number of times of described multi-pass deformation is 3 times.
The deformation of described deformed austeaite tissue and deformation ferritic structure is all carried out on intelligent control swaging rolling plant, and heating, conveying, distortion and experimental parameter are all realized by Controlling System.
Described heating is all adopt induction heating mode.
Embodiment 6:
Tool, across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: the alloying element comprising mass percent wt% as described in Table 3.
The chemical composition of table 3 test steel alloy:
Tool is as follows across the microstructure modulation process of the heat-resisting alloy steel of yardstick heterogeneous In-sltu reinforcement effect:
S1, heat-resisting alloy steel examination is heated to 1200 DEG C and makes its austenitizing, except the carbon of Ti, nitride, all the other alloying elements are solid-solution in austenite completely, then air cooling to 1050 DEG C carries out High Temperature Pre distortion, deflection is 35%, rate of deformation is 0.8/s, forms the deformed austeaite tissue that the carbide of Ti, Nb, nitride or carbonitride strengthen after High Temperature Pre distortion;
S2, air cooling to 900 DEG C is organized to carry out multi-pass deformation the deformed austeaite in S1, the timed interval controlling each passage is 900s and adds in time to vulcanize temperature, distortion total amount is 60%, rate of deformation is 1/s, form the deformation ferritic structure of the carbide of Ti, Nb, V, nitride or carbonitride dispersion-strengthened after multi-pass deformation, and air cooling is to room temperature;
S3, carry out modifier treatment to the deformation ferritic structure in S2, quenching temperature is 890 DEG C, and soaking time is 2 hours, and water-cooled is to room temperature; Tempering temperature is 650 DEG C, and tempering time is 4h, and air cooling is to room temperature.
Described deformed austeaite tissue and deformation ferritic structure are original position phase-change product, are distributed on ferrite matrix between disperse phase, yardstick be nanometer to submicron across yardstick compound; Nanoscale wild phase comprises the multiple combination of MX type carbon, nitride, and it is of a size of 50nm; Submicron-scale wild phase comprises the combination of Me3C, Me23C6, Me7C3, Me2C and MeC type carboritride, and it is of a size of 300nm; M represents metal element Ti in alloying element, Nb, V and Mo, and X represents carbon or nitrogen element, and C represents carbon, and Me represents metallic element Fe, Cr, Mo in alloying element.
The multiple combination of described MX type carbon, nitride comprises TiN, TiC, NbC, NbN, Ti (C, N), Nb (C, N), VN, VC, V (C, N), (Ti, Mo) C, (Ti, Mo) N or (Ti, Mo) (C, N).
The number of times of described multi-pass deformation is 3 times.
The deformation of described deformed austeaite tissue and deformation ferritic structure is all carried out on intelligent control swaging rolling plant, and heating, conveying, distortion and experimental parameter are all realized by Controlling System.
Described heating is all adopt induction heating mode.
Comparative example: adopt conventional martensitic high temperature steel, its alloying element mass percent wt% is in table 4.
The chemical composition of table 4 comparative example martensite heat-resistant steel:
The complete processing step of comparative example steel is as follows:
S1, above-mentioned martensite heat-resistant steel is heated to 1150 DEG C of insulation 1h, air cooling to 1000 DEG C carries out thermal distortion, and deflection is 60%, after being deformed into final size, and air cooling is to room temperature;
S2, sample is heated to 1000 DEG C of insulation 30min, shrend is to room temperature;
S3, sample after quenching is heated to 650 DEG C of tempering, tempering time is 2h.
Described heating adopts induction heating mode.
Performance test is carried out to the steel alloy sample of embodiment 1 ~ 6 and the preparation of contrast row: according to GB GB/T228.1-2010 and GB/T4338-2006 test sample room temperature and high temperature tensile properties, test result is as shown in table 5.
The normal temperature of table 5 steel alloy and mechanical behavior under high temperature
As can be seen from Table 5, sample is after this processes, compared with conventional machining process (i.e. comparative example), under room temperature, mechanical property promotes to some extent, its mechanical behavior under high temperature promotes comparatively obvious, it is 30% that 700 DEG C of tensile strength promote maximum amplitude, it is 47% that yield strength promotes maximum amplitude, show the high-temperature stability that obviously can promote material structure and mechanical property in sample prepared by this technique across the equally distributed carboritride of yardstick disperse, this technique is to heavy duty, the low-carbon alloy steel structure property control technique of being on active service under the severe condition operating modes such as high speed and high temperature has reference and directive significance, there is good popularizing application prospect.
The above is only the preferred embodiment of the present invention; be noted that for those skilled in the art; under the premise without departing from the principles of the invention, can also make some improvements and modifications, these improvements and modifications also should be considered as protection scope of the present invention.
Claims (9)
1. tool is across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: the alloying element comprising following mass percent wt%: C:0.20 ~ 0.45, Mn:1.0 ~ 2.0, Cr:2.0 ~ 4.0, Ni:1.5 ~ 3.0, Ti:0.3 ~ 0.8, Mo:0.01 ~ 0.1, Cu:0.2 ~ 0.8, N:0.005 ~ 0.015, RE:0.001 ~ 0.008, P :≤0.005, S:0.005 ~ 0.01; Also comprise any one or two kinds in V, Nb, V and Nb content summation is 0.05 ~ 0.3; Surplus is Fe and inevitable impurity.
2. tool according to claim 1 is across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: the mass percent of V and Nb is respectively V:0.02 ~ 0.15wt%, Nb:0.01 ~ 0.15wt%.
3. tool according to claim 2 is across the refractory alloy composition of steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: aforesaid alloying element forms heat-resisting alloy steel through refining rolling.
4. the tool according to any one of claim 1 ~ 3, across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, is characterized in that: comprise the following steps:
S1, heat-resisting alloy steel examination is heated to 1100 ~ 1200 DEG C and makes its austenitizing, except the carbon of Ti, nitride, all the other alloying elements are solid-solution in austenite completely, then High Temperature Pre distortion is carried out in air cooling to 950 ~ 1050 DEG C, deflection is 15% ~ 35%, rate of deformation is 0.1/s ~ 0.8/s, forms the deformed austeaite tissue that the carbide of Ti, Nb, nitride or carbonitride strengthen after High Temperature Pre distortion;
S2, air cooling to 850 ~ 900 DEG C are organized to carry out multi-pass deformation the deformed austeaite in S1, the timed interval controlling each passage is 80 ~ 900s and adds in time to vulcanize temperature, distortion total amount is 20% ~ 60%, rate of deformation is 0.2/s ~ 1/s, form the deformation ferritic structure of the carbide of Ti, Nb, V, nitride or carbonitride dispersion-strengthened after multi-pass deformation, and air cooling is to room temperature;
S3, carry out modifier treatment to the deformation ferritic structure in S2, quenching temperature is 870 ~ 890 DEG C, and soaking time is 0.5 ~ 2 hour, and water-cooled is to room temperature; Tempering temperature is 550 ~ 650 DEG C, and tempering time is 1 ~ 4h, and air cooling is to room temperature.
5. tool according to claim 4 is across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: described deformed austeaite tissue and deformation ferritic structure are original position phase-change product, be distributed between disperse phase on ferrite matrix, yardstick be nanometer to submicron across yardstick compound; Nanoscale wild phase comprises the multiple combination of MX type carbon, nitride, and it is of a size of 3 ~ 50nm; Submicron-scale wild phase comprises the combination of Me3C, Me23C6, Me7C3, Me2C and MeC type carboritride, and it is of a size of 100 ~ 300nm; M represents metal element Ti in alloying element, Nb, V and Mo, and X represents carbon or nitrogen element, and C represents carbon, and Me represents metallic element Fe, Cr, Mo in alloying element.
6. tool according to claim 4 is across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: the multiple combination of described MX type carbon, nitride comprises TiN, TiC, NbC, NbN, Ti (C, N), Nb (C, N), VN, VC, V (C, N), (Ti, Mo) C, (Ti, Mo) N or (Ti, Mo) (C, N).
7. tool according to claim 4 is across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: the number of times of described multi-pass deformation is at least 3 times.
8. tool according to claim 4 is across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: the deformation of described deformed austeaite tissue and deformation ferritic structure is all carried out on intelligent control swaging rolling plant, heating, conveying, distortion and experimental parameter are all realized by Controlling System.
9. tool according to claim 4 is across the microstructure modulation process of the heat-resisting alloy steel of the heterogeneous In-sltu reinforcement effect of yardstick, it is characterized in that: described heating is all adopt induction heating mode.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2021121021A1 (en) * | 2019-12-19 | 2021-06-24 | 广东省科学院材料与加工研究所 | Cr-ni austenitic heat-resistant steel with endogenous precipitated reinforced phase, preparation method therefor and use thereof |
| CN113231648A (en) * | 2021-04-29 | 2021-08-10 | 西安建筑科技大学 | High-strength austenitic stainless steel and preparation method thereof |
| CN114480906A (en) * | 2022-02-09 | 2022-05-13 | 江苏硕展精密机械有限公司 | Tungsten carbide particle composite wear-resistant steel plate and manufacturing process thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1557984A (en) * | 2004-01-18 | 2004-12-29 | 江苏省机电研究所有限公司 | High hardness high ductility wear-resistant steel |
| JP2006089796A (en) * | 2004-09-22 | 2006-04-06 | Japan Fine Ceramics Center | Oxidation resistant unit and oxidation resistant coating material |
| CN103146997A (en) * | 2013-03-28 | 2013-06-12 | 宝山钢铁股份有限公司 | Low-alloy high-toughness wear resistant steel plate and manufacturing method thereof |
-
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1557984A (en) * | 2004-01-18 | 2004-12-29 | 江苏省机电研究所有限公司 | High hardness high ductility wear-resistant steel |
| JP2006089796A (en) * | 2004-09-22 | 2006-04-06 | Japan Fine Ceramics Center | Oxidation resistant unit and oxidation resistant coating material |
| CN103146997A (en) * | 2013-03-28 | 2013-06-12 | 宝山钢铁股份有限公司 | Low-alloy high-toughness wear resistant steel plate and manufacturing method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2021121021A1 (en) * | 2019-12-19 | 2021-06-24 | 广东省科学院材料与加工研究所 | Cr-ni austenitic heat-resistant steel with endogenous precipitated reinforced phase, preparation method therefor and use thereof |
| CN113231648A (en) * | 2021-04-29 | 2021-08-10 | 西安建筑科技大学 | High-strength austenitic stainless steel and preparation method thereof |
| CN114480906A (en) * | 2022-02-09 | 2022-05-13 | 江苏硕展精密机械有限公司 | Tungsten carbide particle composite wear-resistant steel plate and manufacturing process thereof |
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Application publication date: 20151216 Assignee: CHANGSHU LONGTENG SPECIAL STEEL Co.,Ltd. Assignor: NANJING INSTITUTE OF TECHNOLOGY Contract record no.: X2022980006877 Denomination of invention: Heat resistant alloy steel with cross scale multiphase in-situ strengthening effect and its microstructure control process Granted publication date: 20170301 License type: Common License Record date: 20220606 |
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