CN117904538A - Impact-resistant and wear-resistant titanium alloy steel and preparation method thereof - Google Patents
Impact-resistant and wear-resistant titanium alloy steel and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 145
- 239000010959 steel Substances 0.000 title claims abstract description 145
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 26
- 238000002360 preparation method Methods 0.000 title abstract description 7
- 238000005096 rolling process Methods 0.000 claims abstract description 43
- 239000010936 titanium Substances 0.000 claims abstract description 31
- 238000010438 heat treatment Methods 0.000 claims abstract description 29
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 24
- 238000004519 manufacturing process Methods 0.000 claims abstract description 22
- 239000000126 substance Substances 0.000 claims abstract description 17
- 239000012535 impurity Substances 0.000 claims abstract description 14
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 12
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 12
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 12
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 11
- 230000035939 shock Effects 0.000 claims abstract description 4
- 229910001566 austenite Inorganic materials 0.000 claims description 28
- 238000001816 cooling Methods 0.000 claims description 23
- 229910000859 α-Fe Inorganic materials 0.000 claims description 19
- 238000001953 recrystallisation Methods 0.000 claims description 17
- 229910000734 martensite Inorganic materials 0.000 claims description 14
- 229910052799 carbon Inorganic materials 0.000 claims description 12
- 229910001563 bainite Inorganic materials 0.000 claims description 11
- 238000005266 casting Methods 0.000 claims description 11
- 230000006835 compression Effects 0.000 claims description 9
- 238000007906 compression Methods 0.000 claims description 9
- 238000003723 Smelting Methods 0.000 claims description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 8
- 238000007670 refining Methods 0.000 claims description 8
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 7
- 238000001556 precipitation Methods 0.000 claims description 6
- 238000005452 bending Methods 0.000 claims description 5
- 230000000717 retained effect Effects 0.000 claims description 4
- 239000007788 liquid Substances 0.000 claims description 2
- 238000005299 abrasion Methods 0.000 abstract description 8
- 239000011159 matrix material Substances 0.000 abstract description 6
- 239000002245 particle Substances 0.000 abstract description 6
- 239000011651 chromium Substances 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 13
- 238000000034 method Methods 0.000 description 12
- 230000008569 process Effects 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 11
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 230000009466 transformation Effects 0.000 description 8
- 229910001562 pearlite Inorganic materials 0.000 description 7
- 239000000203 mixture Substances 0.000 description 6
- 229910052750 molybdenum Inorganic materials 0.000 description 6
- 238000005098 hot rolling Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000009740 moulding (composite fabrication) Methods 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 238000003303 reheating Methods 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910001018 Cast iron Inorganic materials 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000004512 die casting Methods 0.000 description 2
- 238000007599 discharging Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910000604 Ferrochrome Inorganic materials 0.000 description 1
- 229910000616 Ferromanganese Inorganic materials 0.000 description 1
- 229910000519 Ferrosilicon Inorganic materials 0.000 description 1
- 229910001200 Ferrotitanium Inorganic materials 0.000 description 1
- 229910034327 TiC Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- -1 carburant Inorganic materials 0.000 description 1
- 239000004568 cement Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000001186 cumulative effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 230000016507 interphase Effects 0.000 description 1
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 229910052702 rhenium Inorganic materials 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 238000004781 supercooling Methods 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention discloses impact-resistant and wear-resistant titanium alloy steel and a preparation method thereof, and belongs to the field of high-strength hot continuous steel rolling. The shock-resistant and wear-resistant titanium alloy steel comprises the following chemical components in percentage by mass ：C 0.08～0.18％,Si 0.30～0.60％,Mn 1.50～2.00％,P≤0.020％,S≤0.008％,Als 0.020～0.045％,Ti 0.40～0.60％,Cr 0.01～0.50％,N≤0.0050％, and the balance of Fe and unavoidable impurities. The wear-resistant steel provided by the invention has the advantages that the wear-resistant performance of the matrix is reinforced by the micro TiC particles, a new thought that the conventional continuous casting-hot continuous rolling process is adopted to produce the wear-resistant steel without heat treatment is provided, and the problems that the existing wear-resistant steel is high in production cost and can not have wear-resistant performance and impact abrasion resistance can be effectively solved.
Description
Technical Field
The invention belongs to the field of high-strength hot continuous rolling steel, relates to a production method of high-strength hot continuous rolling steel, and in particular relates to impact-resistant and wear-resistant titanium alloy steel and a preparation method thereof.
Background
The traditional wear-resistant steel is produced by adopting a substrate strengthening thought, namely by adding a large amount of hardenability elements and adopting a rolling or forging mode and combining a quenching-tempering heat treatment process.
CN115449702B discloses a preparation method of high-titanium wear-resistant steel, which comprises the steps of mixing, heating and melting waste steel, carburant, ferrochrome and ferrosilicon in an electric furnace, adding ferromanganese after molten steel is melted, heating to 1622-1636 ℃, adding 0.08-0.10% of aluminum accounting for the mass fraction of molten steel in the furnace, controlling the chemical composition and mass fraction of molten steel in the furnace to be 0.69-0.77% of C,1.68-1.85% of Si,2.22-2.48% of Mn,0.65-0.79% of Cr,0.035% of S,0.040% of P,0.03-0.06% of Al and the balance of Fe and unavoidable impurities, then adding ferrotitanium accounting for 0.8-1.0% of the mass fraction of molten steel in the furnace, pouring molten steel into castings after out-of the furnace treatment, reheating the castings to 910-935 ℃, discharging the castings to the temperature of 260-300 ℃ after 2-3 hours, reheating to 320-350 ℃, maintaining the temperature for 8-10 hours, discharging the castings to 150 ℃ until the temperature is lower than 150 ℃ and cooling the high-temperature wear-resistant steel. The invention adopts the production process of electric furnace smelting, casting and heat treatment, the component design adopts higher C, al, mn, ti content, the component design is difficult to meet the production process flow of continuous casting-hot continuous rolling, mainly because the alloy content is high, the casting blank segregation is difficult to control, the Al and Ti content is high, a large amount of Al and Ti inclusions are formed during continuous casting, and a water gap can be blocked.
CN109706399B discloses a high titanium wear-resistant steel and a preparation method thereof, which is characterized by comprising the following steps: electric furnace smelting, LF refining, VD refining, die casting, hot rolling and heat treatment; the wear-resistant steel comprises the following components in percentage by weight: 0.15 to 0.28 percent, si:0.18 to 0.22 percent, mn:0.9 to 1.5 percent, S is less than or equal to 0.015 percent, P is less than or equal to 0.020 percent, mo:0.15 to 0.32 percent, ti:0.30 to 0.6 percent, als: 0.02-0.06%, and the balance of Fe and unavoidable impurities. The heat treatment step is quenching at 800-960 ℃ and tempering at 100-240 ℃. The invention adopts the technological processes of electric furnace smelting, die casting, rolling and heat treatment, the heat treatment is needed, the process cost is high, and meanwhile, 0.15 to 0.32 percent of Mo element is added in the invention, so the alloy cost is high.
CN110055462B discloses a double-scale TiC particle composite reinforced low alloy super wear-resistant steel and a manufacturing method thereof, wherein the chemical composition comprises C：0.18～0.60％、Si：0.30～1.20％、Mn：1.00～3.00％、Cr：0.20～0.40％、Ti：0.2～1.00％、Mo：0.10～0.50％、B：0.0005～0.003％、S：≤0.005％、P：≤0.015, weight percent of iron and unavoidable impurity elements as the rest; wherein, the content of C, ti is more than or equal to 0.10 percent and less than or equal to C percent and less than or equal to 0.40 percent of Ti percent/4; the low alloy super wear-resistant steel contains uniformly distributed micro-scale TiC particles and nano-scale TiC particles. The preparation method of the super wear-resistant steel comprises the steps of smelting, solidification forming, rolling, cooling and heat treatment. The steel of the invention needs to be subjected to heat treatment, the process cost is high, and meanwhile, 0.10 to 0.50 percent of Mo element is added into the steel, so that the alloy cost is high. In addition, the steel has good wear resistance, but does not have good impact wear resistance.
The invention discloses a wear-resistant steel with good forming and welding performance and a production method thereof, and discloses a wear-resistant steel with good forming and welding performance and a production method thereof, wherein the chemical components of the wear-resistant steel are ：Ti:0.20-0.50％,Mn:1.20-1.50％,Si:0.1-0.3％,Als:0.01-0.04％,Mo:0.18-0.22％,P≤0.010％,S≤0.005％,N≤0.0043％,[C] between [ Ti ]/4- [ Ti ]/4+0.05% by weight, ceq is less than or equal to 0.4%, and the balance is iron and other unavoidable impurities. Adopts the production flow of converter smelting, LF refining, RH refining, continuous casting and hot continuous rolling. The steel has good wear resistance, but does not have good impact wear resistance.
CN108374115B discloses an iron-based composite wear-resistant steel reinforced by (V, ti) C particles, and a manufacturing method thereof, wherein the chemical components of the wear-resistant steel are composed of the following components (by weight) ：C 2.0～3.0％,Mn 0.4～0.8％,Si 0.5～0.8％,Cr 3.0～5.0％,V4.64～9.0％,Ti 0～4.36％,Mo 2.0～4.0％,Re 0.05～0.2％,P≤0.07％,S≤0.07％,, and the balance is Fe and unavoidable impurities. The wear-resistant steel obtained by the invention has good impact toughness and higher hardness, and can achieve the following mechanical properties: the hardness HRC is more than or equal to 65, the tensile strength sigma b is more than or equal to 1600Mpa, the impact toughness Aku is more than or equal to 60J/cm < 2 >, the wear resistance is 3-4 times of that of high-chromium cast iron (Cr 26), the defects of high brittleness, easy breaking and fracture in use and lower production cost of the high-chromium cast iron are overcome. The steel belongs to the field of cast steel, the content of alloy elements such as C, cr, V, mo in the chemical components is extremely high, and the steel is difficult to produce by a continuous casting-hot rolling process flow due to casting blank segregation.
In summary, most of the titanium alloyed wear-resistant steels are produced through electric furnace smelting-die casting-heat treatment processes at present, the production efficiency is low, heat treatment is needed, the process cost is high, and meanwhile, most of the titanium alloyed wear-resistant steels are added with elements with high alloy cost such as Mo and the like, and in addition, most of the titanium alloyed wear-resistant steels have good wear resistance but do not have good impact and wear resistance. Therefore, development of steel which can be produced by a continuous casting-hot continuous rolling process, has high production efficiency, does not need heat treatment, does not add high-cost elements such as Mo and the like, and has wear resistance and impact abrasion resistance is needed.
Disclosure of Invention
The invention aims to solve the technical problems that the existing wear-resistant steel is high in production cost and cannot have wear resistance and impact abrasion resistance.
The technical scheme adopted for solving the technical problems is as follows: the shock-resistant and wear-resistant titanium alloy steel comprises the following chemical components in percentage by mass ：C 0.08～0.18％,Si 0.30～0.60％,Mn 1.50～2.00％,P≤0.020％,S≤0.008％,Als 0.020～0.045％,Ti 0.40～0.60％,Cr 0.01～0.50％,N≤0.0050％, and the balance of Fe and unavoidable impurities.
Further, the chemical components in percentage by mass are as follows: 0.10 to 0.16 percent of C, 0.40 to 0.50 percent of Si, 1.50 to 1.80 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.005 percent of S, 0.40 to 0.60 percent of Ti, 0.01 to 0.40 percent of Cr, less than or equal to 0.0040 percent of N, and the balance of Fe and unavoidable impurities.
Further, the yield strength R el is more than or equal to 600MPa, the tensile strength R m is more than or equal to 800MPa, the yield ratio is less than or equal to 0.90, the uniform elongation A gt is more than or equal to 8%, the elongation A is more than or equal to 18%, the impact energy at-20 ℃ is more than or equal to 80J, and the 180-DEG cold bending d=a is not cracked.
Further, the microstructure of the anti-impact and anti-wear titanium alloy steel is 50-75% of ferrite, 20-40% of martensite or bainite, 5-10% of residual austenite, the average grain size is less than or equal to 10 mu m, the TiC precipitated phase size is 1-5 mu m, and the liquid-out TiN size is less than or equal to 5 mu m.
When preparing the anti-impact and anti-wear titanium alloy steel, the anti-impact and anti-wear titanium alloy steel is prepared according to chemical components of the anti-impact and anti-wear titanium alloy steel, and a steel billet is obtained after smelting, refining and casting in a converter or an electric furnace. Heating a steel billet, performing two-stage rolling, performing laminar cooling after rolling, and coiling according to different coiling temperatures after cooling to obtain finished steel with different microstructures; the heating temperature of the steel billet is controlled to be more than or equal to 1220 ℃, the finishing temperature is 830-890 ℃, the thickness of the rolled steel plate is 2-16 mm, and the laminar cooling rate is more than or equal to 15 ℃/s.
Further, the heating temperature is controlled to be 1240-1260 ℃, the finishing temperature is controlled to be 850-870 ℃, and the laminar cooling rate is more than or equal to 20 ℃/s.
Further, the two-stage rolling is a recrystallization zone rolling and a non-recrystallization zone rolling, and the rolling accumulated compression ratio of the recrystallization zone is controlled to be equal to or more than 4, and the rolling accumulated compression ratio of the non-recrystallization zone is controlled to be equal to or more than 4.
Further, the coiling temperature is controlled to be 400-550 ℃, preferably 480-520 ℃, and finished steel with ferrite, bainite and residual austenite microstructure is obtained; the coiling temperature is controlled to be 200-350 ℃, preferably 200-300 ℃, and the finished steel with the microstructure of ferrite, martensite and retained austenite is obtained.
The beneficial effects of the invention are as follows: (1) The wear-resistant steel provided by the invention has the advantages that the wear-resistant performance of the matrix is reinforced by the micro TiC particles, and a new idea of producing the wear-resistant steel by adopting a conventional continuous casting-hot continuous rolling process is provided, and heat treatment is not required. (2) The steel provided by the invention adopts low-cost alloys such as Si, ti and the like, and has lower production cost. (3) The steel provided by the invention has low yield ratio and high elongation, and is easier to form compared with the traditional martensite-based wear-resistant steel. (4) The steel provided by the invention has high low-temperature impact energy, the microstructure contains the residual austenite phase, under the working conditions of high impact and high abrasion, the residual austenite phase is easy to be converted into martensite, the impact energy is absorbed, and a large number of dislocation can be formed in a matrix structure, so that the impact resistance of the material is improved, and the steel is suitable for application scenes such as a cylinder body of a cement tank truck, a lining plate of a ball mill and the like.
Drawings
FIG. 1 is a graph showing the abrasion resistance of comparative steels according to examples of the present invention.
Detailed Description
The technical scheme of the invention can be implemented in the following way.
The shock-resistant and wear-resistant titanium alloy steel comprises the following chemical components in percentage by mass ：C 0.08～0.18％,Si 0.30～0.60％,Mn 1.50～2.00％,P≤0.020％,S≤0.008％,Als 0.020～0.045％,Ti 0.40～0.60％,Cr 0.01～0.50％,N≤0.0050％, and the balance of Fe and unavoidable impurities.
Further, the chemical components in percentage by mass are as follows: 0.10 to 0.16 percent of C, 0.40 to 0.50 percent of Si, 1.50 to 1.80 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.005 percent of S, 0.40 to 0.60 percent of Ti, 0.01 to 0.40 percent of Cr, less than or equal to 0.0040 percent of N, and the balance of Fe and unavoidable impurities.
Further, the yield strength R el is more than or equal to 600MPa, the tensile strength R m is more than or equal to 800MPa, the yield ratio is less than or equal to 0.90, the uniform elongation A gt is more than or equal to 8%, the elongation A is more than or equal to 18%, the impact energy at-20 ℃ is more than or equal to 80J, and the 180-DEG cold bending d=a is not cracked.
Further, the microstructure of the anti-impact and anti-wear titanium alloy steel is 50-75% of ferrite, 20-40% of martensite or bainite, 5-10% of residual austenite, the average grain size is less than or equal to 10 mu m, the TiC precipitated phase size is 1-5 mu m, and the liquid-out TiN size is less than or equal to 5 mu m.
The reasons for the limitation of the main alloying elements in the steel according to the invention will be explained below.
C is an important strengthening element in steel, and is also a constituent element of matrix structures such as bainite and martensite, and when the content of C is low, the proportion of the structures such as bainite and martensite may be reduced, and the strength may be lowered. Meanwhile, elements C and Ti are nucleated at an austenite grain boundary at the final stage of molten steel solidification to form net-shaped micro TiC, the net-shaped micro TiC is crushed and homogenized after the subsequent slab rolling and is uniformly distributed in a matrix structure, and the micro TiC has high hardness and can enhance the wear resistance of the matrix structure. However, the C content is not too high, otherwise, abnormal tissues such as cementite and the like are easy to form, and the toughness and plasticity of the material are reduced. Therefore, the invention controls the C content to be 0.08-0.18%.
Mn can be completely dissolved in austenite, and can play roles in solid solution strengthening and toughness improvement, but when the Mn content is too high, casting blank segregation is easily caused, and the structure uniformity is affected, so that the Mn content is controlled to be 1.50-2.00%.
Si can reduce the austenite phase region in steel, improve Ac3 and Ms points, reduce phase transformation driving force and shear resistance, improve the activity of C in the phase transformation process, promote C to diffuse from ferrite to residual austenite, and play roles in purifying ferrite and enriching carbon in austenite, thereby improving the stability of the residual austenite; meanwhile, si element inhibits nucleation and precipitation of carbide, so that a pearlite transformation curve of 'C' is shifted to the right, and pearlite formation is inhibited. Therefore, the present invention requires the addition of 0.30 to 0.60% Si.
Ti has active chemical property, and can be combined with C, N elements to form a second phase in the whole process of continuous casting-hot rolling, wherein at the final stage of solidification, ti and C can form micron-sized TiC, and Ti and N can form micron-sized liquid-out TiN; in the slab heating stage, ti and C can form submicron solid precipitation TiC; in the finish rolling, laminar cooling and coiling stages, ti and C can form nano TiC through deformation induction precipitation, interphase precipitation and ferrite supersaturation precipitation. Wherein, micron-sized and submicron-sized TiC can play a role in improving the wear resistance in steel, and nano-sized TiC has small influence on the wear resistance due to the small size, but can improve the strength of the steel. Therefore, the present invention requires the addition of 0.40 to 0.60% Ti to form micro-sized TiC to improve the wear resistance of the steel.
Cr can improve the hardenability of steel and promote the structure refinement in the phase transformation process, the thickness of the titanium alloyed wear-resistant steel is 2-16 mm, and Cr element is properly added when the product with the thickness of 10-16 mm is produced so as to improve the cooling uniformity and the structure uniformity of the thick specification. Therefore, the present invention requires the addition of 0.01 to 0.50% Cr.
P, S, N is a common impurity element in steel, and when the P content is higher, the impurity element is easy to gather at a grain boundary, so that the toughness and plasticity of the material are reduced; the S content is higher, so that strip inclusions are easy to form, and the transverse impact toughness of the steel is affected; the N content is higher and is easy to combine with Ti to form liquation TiN, and the forming property of the material is reduced. Therefore, the invention limits P to less than or equal to 0.020%, S to less than or equal to 0.008%, and N to less than or equal to 0.0050%.
When preparing the anti-impact and anti-wear titanium alloy steel, the anti-impact and anti-wear titanium alloy steel is prepared according to chemical components of the anti-impact and anti-wear titanium alloy steel, and a steel billet is obtained after smelting, refining and casting in a converter or an electric furnace. Heating a steel billet, performing two-stage rolling, performing laminar cooling after rolling, and coiling according to different coiling temperatures after cooling to obtain finished steel with different microstructures; the heating temperature of the steel billet is controlled to be more than or equal to 1220 ℃, the finishing temperature is 830-890 ℃, the thickness of the rolled steel plate is 2-16 mm, and the laminar cooling rate is more than or equal to 15 ℃/s.
Further, the heating temperature is controlled to be 1240-1260 ℃, the finishing temperature is controlled to be 850-870 ℃, and the laminar cooling rate is more than or equal to 20 ℃/s.
Further, the two-stage rolling is a recrystallization zone rolling and a non-recrystallization zone rolling, and the rolling accumulated compression ratio of the recrystallization zone is controlled to be equal to or more than 4, and the rolling accumulated compression ratio of the non-recrystallization zone is controlled to be equal to or more than 4.
Further, the steel of the invention comprises two tissue types: the coiling temperature is controlled to be 400-550 ℃, preferably 480-520 ℃, and finished steel with the microstructure of ferrite, bainite and residual austenite is obtained; the coiling temperature is controlled to be 200-350 ℃, preferably 200-300 ℃, and the finished steel with the microstructure of ferrite, martensite and retained austenite is obtained.
The reasons for the limitation of the production process of the impact-resistant and abrasion-resistant titanium alloy steel according to the present invention will be described below.
In order to promote the full solid solution of microalloy elements such as Mn, cr, ti and the like in steel, a higher slab heating temperature is adopted, and at the same time, the proper increase of the slab heating temperature can promote the proper dissolution of the netlike TiC formed at the end of continuous casting, thereby being beneficial to the conversion of the micron TiC form into a spherical form, and at the same time, the proper increase of the slab heating temperature can also alleviate the subsequent rolling compounding and be beneficial to the crushing and homogenization process of the netlike TiC. However, when the heating temperature is too high, austenite grains are coarse. Therefore, the invention controls the reheating temperature of the slab to be more than or equal to 1220 ℃, preferably 1240-1260 ℃.
The main purpose of recrystallization zone rolling is to refine austenite grains by recrystallization, when the rolling deformation is low, the steel billet core is not deformed under sufficient pressure, dynamic recrystallization cannot be started, and austenite is easily grown, so that the grains are coarsened. Meanwhile, the rolling deformation is properly increased, so that the crushing and homogenization of micron-sized reticular TiC in the plate blank can be promoted. Therefore, the invention limits the rolling accumulated compression ratio of the recrystallization zone to be more than or equal to 4.
The main purpose of non-recrystallized zone rolling is to fully flatten the austenite and provide sufficient nucleation sites for subsequent ferrite transformation, thereby refining the grains. Thus, the present invention requires the cumulative compression ratio to be controlled at a higher level, specifically defined as ≡4.
The primary purpose of laminar cooling is to regulate the final tissue morphology by controlling the phase change. In order to obtain a fine and uniform structure so as to ensure the toughness of the steel, a relatively fast laminar cooling rate is required, and meanwhile, the steel also comprises a proper amount of bainite or martensite and a small amount of residual austenite, wherein the types of the structures are low-temperature transformation structures, and the steel can be obtained only by adopting a relatively fast cooling rate and a relatively large supercooling degree and improving the austenite stability of the steel. Thus, the present invention limits the cooling rate to 15 ℃/s or more, preferably 20 ℃/s or more.
The technical scheme and effect of the present invention will be further described by practical examples.
Examples
Table 1 shows the components of the examples and comparative examples of the present invention, and Table 2 shows the production process parameters of the examples and comparative examples of the present invention.
TABLE 1 chemical composition/wt%
TABLE 2 Hot Rolling Process parameters
The steel composition in the embodiment A-embodiment F of the invention meets the requirements of the invention, and after hot continuous rolling, laminar cooling, coiling and other technological parameters are strictly controlled, the finished steel plate is obtained, the yield strength R el is more than or equal to 600MPa, the tensile strength R m is more than or equal to 800MPa, the yield ratio is less than or equal to 0.90, the uniform elongation A gt is more than or equal to 8%, the elongation A is more than or equal to 18%, the impact power at-20 ℃ is more than or equal to 80J, and the 180-DEG cold bending d=a is not cracked. The microstructure is 50-75% ferrite, 20-40% martensite or bainite, 5-10% retained austenite, the average grain size is less than or equal to 10 mu m, the TiC precipitated phase size is 1-5 mu m, the liquid precipitated TiN size is less than or equal to 5 mu m, and the wear resistance is equivalent to NM 360. Table 3 shows the mechanical properties and microstructure of the steels of the examples and comparative examples of the present invention, and FIG. 1 shows the comparison of the abrasion resistance of the steels of the examples and comparative examples of the present invention.
TABLE 3 mechanical Properties and microstructure
The comparative example G steel meets the requirements of the invention, but the laminar cooling rate is lower than 12 ℃/s, the required value is more than or equal to 15 ℃/s, the coiling temperature is higher than 605 ℃ and is 200-350 ℃ or 400-550 ℃ higher than the required value of the invention, so that the microstructure of the finished steel G is ferrite and pearlite, the pearlite content is 26%, the ferrite pearlite steel has lower dislocation density and poorer toughness compared with the dual-phase structure steel, and the uniform elongation A gt of the finished steel G is lower than 7.2%, the required value is 8% lower than the required value of the invention, the impact work at-20 ℃ is lower than 30J, and the required value is more than or equal to 80J.
The chemical composition of the comparative example H steel meets the requirements of the invention, but the rolling accumulation compression of a recrystallization zone is lower, namely 3.2, which is lower than the required value of the invention by more than or equal to 4, so that the average grain size of the finished steel H is larger, 11.0 mu m, which is lower than the required value of the invention by less than or equal to 10 mu m, and the low-temperature impact energy of the finished steel H is lower, namely 43J, which is lower than the required value of the invention by more than or equal to 80J, which is caused by coarse grains and poor uniformity of the grains.
The comparative example I steel has a lower Si element content of 0.10% and lower than the required value of 0.30-0.60% in the steel, so that the austenite stability in the steel is insufficient, and therefore, the finished steel microstructure obtained by adopting the controlled rolling and cooling process required by the invention is ferrite and martensite, and no residual austenite structure appears, so that the impact resistance of the steel cannot be improved by deformation induced transformation when the finished steel I is subjected to impact abrasion in the subsequent use process.
The comparative example J steel has a low Ti content of 1.5%, 4.0-6.0% lower than the required value of the invention, and 0.17% Mo is added, and the steel is conventional 800MPa low-alloy high-strength steel. Because the Ti content is low, a large amount of micron-sized TiC cannot be formed in the steel, the wear resistance of the finished steel J is low although various mechanical property indexes are good, and the wear loss weight is far higher than that of the examples A-F, and the specific view is shown in fig. 1.
The C content in the steel composition of the comparative example K is higher than 0.20%, the C content is higher than the required value of the invention by 0.08-0.18%, the coiling temperature is higher than 560 ℃, the C content is higher than the required value of the invention by 400-550 ℃, and the steel enters a pearlite transformation zone, so that a small amount of pearlite tissues appear in the finished steel K, the low-temperature impact energy of the finished steel H is lower than 37J, the C content is lower than the required value of the invention by more than or equal to 80J, and the cold bending test d=a of 180 degrees is cracked.
The comparative example L steel has N content higher than 0.0065% and less than or equal to 0.0050% of the required value of the invention, which results in increased quantity of liquid-out TiN in the steel, increased size of 7.9 μm and less than or equal to 5 μm of the required value of the invention, and further results in lower impact energy of the finished steel at minus 40 ℃ of 52J and less than or equal to 80J of the required value of the invention.
Claims (10)
1. The shock-resistant and wear-resistant titanium alloy steel is characterized by comprising the following chemical components in percentage by mass ：C 0.08～0.18％,Si 0.30～0.60％,Mn 1.50～2.00％,P≤0.020％,S≤0.008％,Als 0.020～0.045％,Ti 0.40～0.60％,Cr 0.01～0.50％,N≤0.0050％, and the balance of Fe and unavoidable impurities.
2. The impact resistant and wear resistant titanium alloyed steel according to claim 1, wherein: 0.10 to 0.16 percent of C, 0.40 to 0.50 percent of Si, 1.50 to 1.80 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.005 percent of S, 0.40 to 0.60 percent of Ti, 0.01 to 0.40 percent of Cr, less than or equal to 0.0040 percent of N, and the balance of Fe and unavoidable impurities.
3. The impact resistant and wear resistant titanium alloyed steel according to claim 1 or 2, wherein: the yield strength R el is more than or equal to 600MPa, the tensile strength R m is more than or equal to 800MPa, the yield ratio is less than or equal to 0.90, the uniform elongation A gt is more than or equal to 8%, the elongation A is more than or equal to 18%, the impact energy at minus 20 ℃ is more than or equal to 80J, and the 180-degree cold bending d=a is not cracked.
4. The impact resistant and wear resistant titanium alloyed steel according to claim 1 or 2, wherein: the microstructure is 50-75% ferrite, 20-40% martensite or bainite, 5-10% retained austenite, the average grain size is less than or equal to 10 mu m, the TiC precipitated phase size is 1-5 mu m, and the liquid precipitation TiN size is less than or equal to 5 mu m.
5. The method for producing an impact-resistant and wear-resistant titanium alloy steel according to any one of claims 1 to 4, wherein: when preparing the anti-impact and anti-wear titanium alloy steel, the anti-impact and anti-wear titanium alloy steel is prepared according to chemical components of the anti-impact and anti-wear titanium alloy steel, and a steel billet is obtained after smelting, refining and casting in a converter or an electric furnace.
6. The method for producing an impact-resistant and wear-resistant titanium alloy steel according to claim 5, wherein: heating a steel billet, performing two-stage rolling, performing laminar cooling after rolling, and coiling according to different coiling temperatures after cooling to obtain finished steel with different microstructures; the heating temperature of the steel billet is controlled to be more than or equal to 1220 ℃, the finishing temperature is 830-890 ℃, the thickness of the rolled steel plate is 2-16 mm, and the laminar cooling rate is more than or equal to 15 ℃/s.
7. The method for producing an impact-resistant and wear-resistant titanium alloy steel according to claim 5, wherein: the heating temperature is controlled to 1240-1260 ℃, the finishing temperature is controlled to 850-870 ℃, and the laminar cooling rate is more than or equal to 20 ℃/s.
8. The method for producing an impact-resistant and wear-resistant titanium alloy steel according to claim 6, wherein: the two-stage rolling is a recrystallization zone rolling and a non-recrystallization zone rolling, wherein the rolling accumulated compression ratio of the recrystallization zone is controlled to be more than or equal to 4, and the rolling accumulated compression ratio of the non-recrystallization zone is controlled to be more than or equal to 4.
9. The method for producing an impact-resistant and wear-resistant titanium alloy steel according to claim 5, wherein: the coiling temperature is controlled to be 400-550 ℃, and finished steel with a microstructure of ferrite, bainite and residual austenite is obtained; and controlling the coiling temperature to be 200-350 ℃ to obtain the finished steel with the microstructure of ferrite, martensite and residual austenite.
10. The method for producing an impact-resistant and wear-resistant titanium alloy steel according to claim 9, wherein: the coiling temperature is controlled to be 480-520 ℃ to obtain finished steel with a microstructure of ferrite, bainite and residual austenite; and controlling the coiling temperature to be 200-300 ℃ to obtain the finished steel with the microstructure of ferrite, martensite and residual austenite.
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