CN104862461A - Preparation method for medium plate containing interphase-precipitated titanium carbide - Google Patents
Preparation method for medium plate containing interphase-precipitated titanium carbide Download PDFInfo
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Abstract
The invention provides a preparation method for a medium plate containing interphase-precipitated titanium carbide. The medium plate comprises the following chemical components in percentage by mass: 0.05 to 0.15 percent of C, 0.15 to 0.40 percent of Si, 1.00 to 2.00 percent of Mn, less than 0.01 percent of P, less than 0.01 percent of S, less than 0.005 percent of N, 0.04 to 0.15 percent of Ti and the balance of Fe and inevitable impurities. According to the preparation method, an inter-phase precipitated medium steel plate with high comprehensive mechanical properties is obtained by reasonably designing the content of alloy element Ti, combining solid solution strengthening and precipitation strengthening effects of the alloy element and adopting a TMCP process and a quenching and tempering process, and has tensile strength of stronger than 600 MPa, yield strength of stronger than 500 MPa and -20 DEG C V-shaped impact energy of more than 47 J.
Description
Technical field
The present invention relates to a kind of micro-alloyed steel of titaniferous, be specifically related to a kind of containing INTERPHASE CARBIDE PRECIPITATION titanium carbide steel plate and preparation method thereof.
Background technology
When adding the strong carbide elements such as V, Nb, Ti, Mo in soft steel, at austenite in ferritic transformation process, alloying element is combined the carbide formed and may distributes along γ/α interface cycle sheet with carbon, this transformation is called as " INTERPHASE CARBIDE PRECIPITATION " or " alternate precipitation ".When observing under the tem, if when the crystallography face at precipitation particles place is parallel with beam direction, the typical pattern of INTERPHASE CARBIDE PRECIPITATION can be observed, i.e. carbide regular distribution in a row on matrix.On the one hand, the ferrite matrix in INTERPHASE CARBIDE PRECIPITATION steel ensures that steel have good toughness; Another important aspect, because tiny Nano-Scaled Carbide is distributed on matrix, therefore can produce powerful precipitation strength effect, thus drastically increase the intensity of steel.2004, the people such as Funakawa lead to controlled rolling and controlled cooling and in the mode of two-phase region isothermal, obtain a kind of full Nanohiten steel for ferritic structure, ferrite matrix is dispersed with the nano-carbide of separating out with INTERPHASE CARBIDE PRECIPITATION, and the precipitation strength of nano-carbide reaches 300MPa.
At present, for alternate precipitation steel, many methods by adding Alloying Element Molybdenum, niobium, vanadium in alloying element component, utilize them in γ/α phase transition process, with the Nano-Scaled Carbide that the form of INTERPHASE CARBIDE PRECIPITATION is separated out on ferrite matrix, thus reach the effect of significant precipitation strength.But the alloying elements such as molybdenum, niobium, vanadium belong to noble metal, and price is higher, therefore substantially increases the production cost of steel plate.In thermal treatment process, after prior art adopts austenitic area rolling, be chilled to γ/α two-phase region soon, by increasing condensate depression, increase INTERPHASE CARBIDE PRECIPITATION forming core point, afterwards in two-phase region isothermal processes, obtain the alternate carbide precipitate of nano level (as application number 201410367193.4 Chinese patent).But the cooling rate of plate of moderate thickness in actual production is no more than 20 DEG C/s usually at present, cannot realize rapid cooling.Up to now, in the production of steel plate, the precipitation strength utilizing INTERPHASE CARBIDE PRECIPITATION is rarely had to be used for improving the report of intensity.This be due to, coiling technique (isothermal processes) is not had in the actual production of plate of moderate thickness, many employings continuous coo1ing technique, and in continuous cooling process, in two-phase region, the residence time is shorter, condensate depression is low, and forming core point is relatively less, and carbide possibly cannot at the regular forming core in γ/α interface.If can design a kind of specific alloy components containing, obtain INTERPHASE CARBIDE PRECIPITATION, and be applied in the actual production of steel plate by specific continuous coo1ing technique, that will obtain the more excellent plate of moderate thickness of a kind of over-all properties.
Summary of the invention
The object of this invention is to provide a kind of preparation method containing INTERPHASE CARBIDE PRECIPITATION titanium carbide steel plate, on the Composition Design basis of low-carbon (LC), by design alloying element content and in conjunction with TMCP technique, the alloying element titanium in steel is made to be combined the carbide formed with carbon, in γ/α transition temperature range in continuous cooling process, separate out with the form of INTERPHASE CARBIDE PRECIPITATION, its size is no more than 10nm, thus significantly improves the intensity of invention steel.Adopt the thermal treatment process of modifier treatment subsequently, improve the low-temperature impact toughness of steel plate further, optimize the tough matching degree of steel plate.
A kind of manufacturing process containing INTERPHASE CARBIDE PRECIPITATION titanium carbide plate of moderate thickness involved in the present invention is as follows:
(1) alloying constituent: the chemical composition containing INTERPHASE CARBIDE PRECIPITATION titanium carbide plate of moderate thickness chosen and each element mass percent are respectively: C:0.05-0.15%, Si:0.15-0.40%, Mn:1.00-2.00%, P<0.01%, S<0.01%, N<0.005%, Ti:0.04%-0.15%, surplus is Fe and inevitable impurity.
(2) rolling technology: adopt γ phase recrystallization zone and Unhydrated cement two-phase control rolling after 1100-1200 DEG C of insulation 1-2h, wherein steel billet start rolling temperature is 1000-1100 DEG C, finishing temperature is 800-880 DEG C, under the stagnation pressure of 75-90% after distortion, steel plate thickness is 10-20mm, be chilled to 550-700 DEG C with 0 ~ 6 DEG C/s cooling rate subsequently, to be phased substantially complete after shrend to room temperature.
(3) thermal treatment process: steel plate is carried out modifier treatment, wherein, quenching temperature is 900-1000 DEG C, shrend after isothermal 30-60min, then at 550-700 DEG C of tempering 30-60min.
In aforesaid method, the steel plate that described step (2) obtains, the size of the carbide particle of separating out in the mode of INTERPHASE CARBIDE PRECIPITATION is between 5-15nm, and this nano-scaled precipitate is TiC.
In aforesaid method, the tensile strength of the plate of moderate thickness of acquisition is greater than 600MPa, and yield strength is greater than 500MPa, the V-type ballistic work >=47J of-20 DEG C.
The effect of each element of the present invention and proportioning according to following (in mass percent for):
Carbon: the principal element of solution strengthening.Along with the raising of carbon content, the alloying element of solid solution in tissue more can be combined with C and form all kinds of carbide.C is combined the carbide of the titaniferous formed with alloying element Ti, and the intensity of precipitation strength effect to steel of these carbide has important contribution.But, when carbon content is too high, not only unfavorable to the impelling strength of steel, and C content more than 0.2% time welding property will be caused to worsen.Therefore, steel of the present invention adopts low-carbon (LC) Composition Design, and carbon content is 0.05-0.15%.
Silicon: deoxidant element conventional in steel, simultaneously can also the effective intensity improving solid solution in steel, but along with the raising of silicone content, and the toughness of steel, plasticity and welding property will constantly worsen.Therefore, the silicone content of steel of the present invention is 0.15-0.40%.
Manganese: manganese is good reductor and sweetening agent, and effectively can also improve hardening capacity and the intensity of steel.But, when Fe content is too high, its in strand segregation tendency increase, the welding property of steel also can be made to degenerate.Consider, the Fe content of steel of the present invention is 1.00-2.00%.
Phosphorus: harmful element in steel, not only destroys the welding property of steel, but also can reduce plasticity, increases the cold shortness of steel.Therefore usually require that in steel, phosphorus content is less than 0.045%, the phosphorus content of steel of the present invention is less than 0.01%.
Sulphur: make steel produce red brittleness, reduces ductility and the toughness of steel, causes crackle when forging and rolling.Sulphur is also unfavorable to welding property, and in steel, sulphur content should be no more than 0.01%.
Nitrogen: being easily combined with Ti and forming TiN, is common being mingled with in microalloyed steel.Because TiN size is comparatively large, both cannot not have the effect of precipitation strength by crystal grain thinning yet, and when the nitrogen content in steel is higher than 0.005wt.%, micron-sized TiN can be formed, the toughness of grievous injury steel plate.Therefore the nitrogen content in steel should control within 0.005wt.%.
Titanium: the key alloying element of steel of the present invention, titanium and carbon, nitrogen have extremely strong avidity, can form TiC, Ti (CN), and wherein TiC particle has the effect stoping grain growth alligatoring in steel, makes Coarsening Temperature be increased to more than 1000 DEG C.In steel of the present invention, the alloying element titanium of high level is combined the Nano-Scaled Carbide formed with carbon, in the operation of rolling, the TiC particle of deformation-induced precipitation has strong inhibition to austenite recrystallization, thus the ferritic structure refinement obtained after making phase transformation, improve the obdurability of steel.In the present invention, steel laboratory of the present invention Gleeble thermal analogy found that, after the rolling of austenitic area in two-phase region with in 0 ~ 6 DEG C/s cooling rate continuous cooling process, the carbide of a large amount of titaniferous when γ → α phase transformation by with the formal distribution of alternate precipitation on ferrite matrix, its size is no more than 10nm, significant precipitation strength effect will be produced, the intensity of the raising invention steel contributed to; Also has the carbide of the titaniferous that supersaturation is separated out from austenite, ferrite in heat treatment process, the intensity of the raising invention steel that this also contributes to simultaneously.Another important aspect, alloying element titanium is relative to niobium, vanadium, molybdenum, and cost is lower.But, when titanium content is more than 0.2%, is easily combined with O, N, S and forms thick inclusion, unfavorable to the toughness of steel.Consider, the scope of the titanium content of steel of the present invention is 0.04%-0.15%.
The feature of the technology controlling and process that the present invention relates to is:
Rolling technology of the present invention adopts recrystallization zone and Unhydrated cement two-phase control rolling.In the austenite recrystallization controlled rolling process of high-temperature zone, suppress the alligatoring of austenite crystal by recrystallize repeatedly, thus obtain tiny austenite structure; In the controlled rolling process of Unhydrated cement, by the distortion in non-recrystallization humidity province to realize the accumulation of being out of shape, a large amount of defects is produced in deformed austenite crystal grain, thus ferritic preferential nucleation site accelerate the diffusion of alloying element when increasing phase transformation.
After rolling, 0 ~ 6 DEG C/s cooling rate continuous coo1ing is to 550-700 DEG C, and the main purpose of controlled cooling model speed adopts alap cooling rate to ensure that the carbide of titaniferous has time enough to carry out INTERPHASE CARBIDE PRECIPITATION in γ/α two-phase region.This is because INTERPHASE CARBIDE PRECIPITATION controls by alloying element and Carbon diffusion, in phase interface moving process, there is enrichment in the solute at interface, when being enriched to a certain degree, phase interface there will be precipitation, but when speed of cooling is too fast, solute atoms has little time enrichment at phase interface place and precipitated phase occurs to become.
After end to be phased, accelerating cooling is in order to further thinning microstructure, and then improves intensity.Carry out modifier treatment to steel of the present invention subsequently, its main purpose improves the low-temperature impact toughness of steel plate further, and then obtain more excellent tough matching degree.
Compared with prior art, its advantage is in the present invention:
(1) Composition Design of high titanium, low-carbon (LC) is adopted, INTERPHASE CARBIDE PRECIPITATION steel conventional high cost Alloying Element Molybdenum, niobium, vanadium is replaced with the alloying element titanium of low cost, by solution strengthening and precipitation strength effect, the yield strength of steel plate of the present invention is made to bring up to more than 500MPa.Therefore, the production cost of steel plate is significantly reduced;
(2) owing to only with the addition of alloying element titanium and manganese, therefore the smelting forging of steel plate is relatively simple;
(3) adopt 0 ~ 6 DEG C/s cooling rate continuous coo1ing technique to replace and obtain the conventional Isothermal Treatment of INTERPHASE CARBIDE PRECIPITATION tissue, and in actual production, air cooling cooling rate is roughly 2 DEG C/s, thus this INTERPHASE CARBIDE PRECIPITATION steel can be applied in the continuous actual production of plate of moderate thickness better;
(4) the INTERPHASE CARBIDE PRECIPITATION carbide size obtained in continuous cooling process is less than 10nm, and after modifier treatment, such Carbide Coarsening speed is low, serves the effect strengthening armor plate strength;
(5) a kind of INTERPHASE CARBIDE PRECIPITATION steel plate with excellent in strength and toughness is produced by TMCP rolling technology+modifier treatment technique, this steel plate can reach following comprehensive mechanical property: tensile strength is greater than 600MPa, yield strength is greater than 500MPa, and the V-type ballistic work of-20 DEG C is more than 47J;
Accompanying drawing explanation
Fig. 1 is the typical shape appearance figure that in embodiment 3, Nano-Scaled Carbide (TiC) is separated out with INTERPHASE CARBIDE PRECIPITATION.
Fig. 2 is the Sjffle dE A typical spectrum of the precipitated phase that Fig. 1 is corresponding, mainly containing Ti, C, Fe, Mn (Fe, Mn are matrix composition).
Embodiment
Specific embodiments of the invention adopt metaloscope (OM) to observe microstructure morphology, and characterize the pattern of precipitated phase in invention steel matrix tissue, distribution and composition in conjunction with FEITecnai G2F20 transmission electron microscope (TEM).
Embodiment 1
Steel embodiment of the present invention is smelted at vacuum induction furnace, and its chemical composition mass percent is respectively: C:0.12%, Si:0.18%, Mn:1.51%, P:0.009%, S:0.009%, N:0.0031%, Ti:0.044%, surplus is Fe and inevitable impurity.
Heating steel billet to 1200 DEG C is incubated 2h, then carries out two-phase control rolling in austenite recrystallization district and Unhydrated cement.Wherein, roughing temperature is 1100 DEG C, and after six passage distortion, steel plate thickness is 12mm, and total reduction is 85%, and finishing temperature is 870 DEG C.After rolling by hardening after steel plate air cooling to 600 DEG C to room temperature.Carry out modifier treatment subsequently: steel plate is heated to shrend after 920 DEG C of isothermal 40min, then at 650 DEG C of tempering 30min.The V-type ballistic work of the tensile strength of embodiment 1 steel plate, yield strength, unit elongation and-20 DEG C is in table 1.
The mechanical property of table 1 steel embodiment 1 of the present invention Ti microalloyed steel
Embodiment 2
Steel embodiment of the present invention is smelted at vacuum induction furnace, and its chemical composition mass percent is respectively: C:0.08%, Si:0.22%, Mn:1.55%, P:0.005%, S:0.002%, N:0.0027%, Ti:0.082%, surplus is Fe and inevitable impurity.
Heating steel billet to 1180 DEG C is incubated 2h, then carries out two-phase control rolling in austenite recrystallization district and Unhydrated cement.Wherein, roughing temperature is 1050 DEG C, and after six passage distortion, steel plate thickness is 12mm, and total reduction is 80%, and finishing temperature is 850 DEG C.After rolling by hardening after steel plate air cooling to 580 DEG C to room temperature.Carry out modifier treatment subsequently: steel plate is heated to shrend after 950 DEG C of isothermal 30min, then at 680 DEG C of tempering 30min.The V-type ballistic work of the tensile strength of embodiment 2 steel plate, yield strength, unit elongation and-20 DEG C is in table 2.
The mechanical property of table 2 steel embodiment 2 of the present invention Ti microalloyed steel
Embodiment 3
Steel embodiment of the present invention is smelted at vacuum induction furnace, and its chemical composition mass percent is respectively: C:0.077%, Si:0.24%, Mn:1.58%, P:0.007%, S:0.002%, N:0.0035%, Ti:0.14%, surplus is Fe and inevitable impurity.
Heating steel billet to 1150 DEG C is incubated 2h, then carries out two-phase control rolling in austenite recrystallization district and Unhydrated cement.Wherein, roughing temperature is 1050 DEG C, and after six passage distortion, steel plate thickness is 12mm, and total reduction is 90%, and finishing temperature is 850 DEG C.After rolling by shrend after steel plate air cooling to 550 DEG C to room temperature.Carry out modifier treatment subsequently: steel plate is heated to shrend after 920 DEG C of isothermal 30min, then at 600 DEG C of tempering 40min.The V-type ballistic work of the tensile strength of embodiment 3 steel plate, yield strength, unit elongation and-20 DEG C is in table 3.
From Fig. 1 and Fig. 2, in matrix, with the nano particle of INTERPHASE CARBIDE PRECIPITATION precipitation, not only size is less, and density is comparatively large, and its composition is TiC, is of a size of 5-15nm.
The mechanical property of table 3 steel embodiment 3 of the present invention Ti microalloyed steel
Claims (3)
1., containing a preparation method for the plate of moderate thickness of INTERPHASE CARBIDE PRECIPITATION titanium carbide, it is characterized in that:
(a) alloying constituent: the chemical composition containing INTERPHASE CARBIDE PRECIPITATION titanium carbide plate of moderate thickness chosen and each element mass percent are respectively C:0.05-0.15%, Si:0.15-0.40%, Mn:1.00-2.00%, P<0.01%, S<0.01%, N<0. 005%, Ti:0.04%-0.15%, surplus is Fe and inevitable impurity;
(b) rolling technology: adopt γ phase recrystallization zone and Unhydrated cement two-phase control rolling after 1100-1200 DEG C is incubated 1-2h, wherein start rolling temperature is 1000-1100 DEG C, finishing temperature is 800-880 DEG C, under the stagnation pressure of 75-90% after distortion, steel plate thickness is 10-20mm, subsequently with 0 ~ 6 DEG C/s cooling rate continuous coo1ing to 550-700 DEG C, to be phased substantially complete after shrend to room temperature;
(c) thermal treatment process: steel plate is carried out modifier treatment, wherein quenching temperature is 900-1000 DEG C, shrend after isothermal 30-60min, then at 550-700 DEG C of tempering 30-60min.
2. the preparation technology containing INTERPHASE CARBIDE PRECIPITATION titanium carbide steel plate according to claim 1, it is characterized in that, the steel plate that described step (b) obtains, the size of the carbide particle of separating out in the mode of INTERPHASE CARBIDE PRECIPITATION is all between 5-15nm, and this nano-scaled precipitate is TiC.
3. the preparation method containing INTERPHASE CARBIDE PRECIPITATION titanium carbide steel plate according to claim 1, it is characterized in that, the tensile strength of the plate of moderate thickness of acquisition is greater than 600MPa, and yield strength is greater than 500MPa, the V-type ballistic work >=47J of-20 DEG C.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108624814A (en) * | 2018-04-28 | 2018-10-09 | 武汉钢铁有限公司 | HB500 grades of cut deal wear-resisting steel plates and manufacturing method |
| CN113881898A (en) * | 2021-09-29 | 2022-01-04 | 广东韶钢松山股份有限公司 | Nano TiC reinforced Ti micro-alloyed steel and preparation process thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101713046A (en) * | 2009-12-14 | 2010-05-26 | 钢铁研究总院 | Preparation method of superfine grain martensitic steel reinforced and controlled by nano precipitated phase |
| CN102676927A (en) * | 2012-06-12 | 2012-09-19 | 钢铁研究总院 | High-Ti micro-alloyed medium thickness steel plate and preparation method thereof |
| CN104032237A (en) * | 2014-05-15 | 2014-09-10 | 合肥通用机械研究院 | Composite microalloyed high-strength steel forging with tensile strength of 700MPa and production method thereof |
-
2015
- 2015-06-03 CN CN201510300961.9A patent/CN104862461B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101713046A (en) * | 2009-12-14 | 2010-05-26 | 钢铁研究总院 | Preparation method of superfine grain martensitic steel reinforced and controlled by nano precipitated phase |
| CN102676927A (en) * | 2012-06-12 | 2012-09-19 | 钢铁研究总院 | High-Ti micro-alloyed medium thickness steel plate and preparation method thereof |
| CN104032237A (en) * | 2014-05-15 | 2014-09-10 | 合肥通用机械研究院 | Composite microalloyed high-strength steel forging with tensile strength of 700MPa and production method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108624814A (en) * | 2018-04-28 | 2018-10-09 | 武汉钢铁有限公司 | HB500 grades of cut deal wear-resisting steel plates and manufacturing method |
| CN113881898A (en) * | 2021-09-29 | 2022-01-04 | 广东韶钢松山股份有限公司 | Nano TiC reinforced Ti micro-alloyed steel and preparation process thereof |
| CN113881898B (en) * | 2021-09-29 | 2022-06-21 | 广东韶钢松山股份有限公司 | Nano TiC reinforced Ti micro-alloyed steel and preparation process thereof |
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