CN104195409A - Method for enhancing strength and toughness of medium-carbon V steel - Google Patents
Method for enhancing strength and toughness of medium-carbon V steel Download PDFInfo
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- CN104195409A CN104195409A CN201410439695.3A CN201410439695A CN104195409A CN 104195409 A CN104195409 A CN 104195409A CN 201410439695 A CN201410439695 A CN 201410439695A CN 104195409 A CN104195409 A CN 104195409A
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Abstract
The invention discloses a method for enhancing strength and toughness of medium-carbon V steel, which comprises the following steps: 1) in the smelting process, adding N to control [C], [V] and [N] in the steel; 2) heating the smelted continuous casting billet until the crystalline VN compound is dissolved back to austenite, and rolling into round steel; 3) keeping the temperature within the maximum precipitation peak value range to precipitate abundant VN particles; and 4) controlling the subsequent cooling rate of the round steel within a certain range so that the particle size of more than 80% of VN precipitated phase in the steel is 20-100nm, thereby obtaining the medium-carbon V steel with higher strength and toughness. By using the influence of the N element on different aspects of steel performance, the minor element component system is designed without modifying the production equipment or greatly adjusting the technique; and the yield strength of the medium-carbon V steel can be enhanced by 80-170 MPa, the ductility and fracture toughness of the steel are well improved, the percentage elongation after fracture A is enhanced by 3-5%, and the ballistic work Aku2 is enhanced by 10-50J.
Description
Technical field
The present invention relates to a kind of production method of middle carbon V steel, particularly a kind of method of carbon V steel obdurability in raising, belongs to iron and steel processing technique field.
Background technology
Middle carbon V (vanadium) steel mainly refers to the steel grades such as 35MnV, 40CrV, 50CrVA, 40MnVB, SAE6140 (ASTM A355 standard), EN51CrV4 (EN10083/1 standard), be used for manufacturing auto parts, mechanical component, spring, instrument etc., Application Areas is very extensive, is characterized in: 1. in steel C content 0.32～0.65%; 2. in steel, V content, 0.10～0.30%, especially concentrates on 0.10～0.20%; 3. before steel application, all need to quench, tempering modifier treatment, thereby require very tight to steel obdurability.
The obdurability of these steel grades is mainly that the means such as the admittedly molten strengthening of closing gold element, aging precipitation strengthening, build up realize, and is specially: add the alloying element of some amount to gain in strength, add V to carry out thin brilliant highly malleablized, material is heat-treated to technique etc.These measures can improve the toughness and tenacity of steel really, but respectively have relative merits, in practical steel, often these enhancement methods will be mutually combined and just can reach desired properties, inevitably will increase cost, operation and time of delivery in steel production process.
V is that reinforced ferrite encloses one of forming element mutually with γ, and it and carbon (C), nitrogen (N), oxygen (O) have extremely strong avidity, forms with it corresponding very stable compound (as V
4c
3, VN, V
2o
3deng), tissue and the crystal grain of main refinement steel in steel, the superheated susceptivity of reduction steel, intensity and the toughness of raising steel.In steel, C content is 0.35～0.65%, and V element and C form V
4c
3compound, this compound is very stable, only has at high temperature and could dissolve in austenite lentamente, therefore though V4C3 energy crystal grain thinning, because its particle size is large, has reduced the toughness of steel on the contrary.Thereby middle carbon V steel generally will be controlled the content (V≤0.50%) of V.
N plays the effect such as solution strengthening, ageing strengthening with formation stable compounds such as Al, Ti, V, Fe in steel, but due to Fe
4n separates out, and causes the phenomenon such as timeliness and blue shortness, super bubble, loose, the defects i.e.cracks of easily forming when many of content.Nitrogen generally with furnace charge enter with smelting process in molten steel absorb from the external world, non-artificial autotelic adding, converter steel [N]: 30～50ppm, electric steel [N]: 50～70ppm ([N] represents the weight ratio concentration of N in steel).
At present, having utilizes VN to improve the document of the character of steel, for example " containing VN, TiN powder rich chromium cast iron, this cast iron preparation method and wearing piece " (patent No.: the forming core core of 201110137773) utilizing VN powder to solidify as rich chromium cast iron molten metal matrix and carbide, improve the wear resistance of foundry goods, play strengthening effect." a kind of production method of VN reinforcing bar of bending the strong degree≤400MPa level of clothes " (patent No.: 201110151235) the VN16 alloy adding is packed in the container that normal quality structural carbon steel makes and after sealing and be placed in ladle, VN16 alloy recovery is improved, the stable mechanical property performance of VN reinforcing bar is better, and product surface quality is improved.And " application of VN alloy in non-hardened and tempered steel " (Lu Xiangyang etc., " steel vanadium titanium ", 03 phase in 2000) article is mainly to have studied: the application of VN alloy in F35MnVN steel, and effect and molten steel increasing method for nitrogen to vanadium, nitrogen is studied.But these documents are all to utilize the VN alloy that adds, replace and reaches solution strengthening by atoms metal, thereby need to add some amount contain V alloy or VN alloy.Due to high containing V alloy or VN alloy price, reach the production technique cost of solution strengthening therefore existing by V atomic substitutions high, a little less than the market competitiveness.In addition on the one hand, after in steel, V content increases, particularly V in steel
4c
3when quantity increase, particle size increase, can reduce on the contrary the toughness of steel.
The inventive method adopts and reduces V content, increase N content, and separate out peak temperature section maintenance certain hour at VN in the operation of rolling, make that VN precipitated phase quantity is many and its particle size is little, thereby strengthen intensity and the toughness of steel, utilize precipitation strength, when reaching the production cost of carbon V steel in reduction, improve the obdurability of steel.
Summary of the invention
The object of the present invention is to provide the method for carbon V steel obdurability in a kind of raising, in improving with the content by V and N in control steel and VN particle size, the obdurability of carbon V steel, reduces production costs, reduces subsequent heat treatment operation.
For achieving the above object, the present invention adopts the novel process of control " V, N content+VN precipitate size, quantity in steel ", by the technical matters such as VN precipitated phase particle size and quantity in V, N constituent content, heating steel billet rolling, round steel in carbon V steel in controlling, thereby reach the obdurability of carbon V steel in raising.
Specifically comprise the following steps:
1) while smelting, add N element, in refining process, be blown into N to molten steel
2gas, and control N content range in steel and, at [N] 0.0070%～0.0120%, make C in steel, V element content range be controlled at: [C] 0.35%～0.65%, [V] 0.10%～0.30% simultaneously; Wherein [C], [V] and [N] represent respectively C, V and the N weight percent concentration in steel;
2) continuously cast bloom that heating obtains after smelting is also incubated 30～75min 1100～1200 DEG C of scopes, makes the VN compound back dissolving of crystalline state in austenite, is rolled into subsequently round steel;
3) separate out peak value scope insulation 1.0～2.0min 850 DEG C ± 20 DEG C maximums, VN particle is separated out in a large number;
4) control round steel subsequently speed of cooling be 0.7～0.95 DEG C/s, make in steel 80% above VN precipitated phase particle size in 20～100nm scope, obtain the middle carbon V steel of obdurability raising.
Further improve described step 1) in, by [V] scope control in steel 0.10%～0.20%; Described step 2) in, heating and temperature control, at 1140 DEG C～1190 DEG C, is incubated to 30～55min.
Further improve again described step 1) in, be [V] by V, N constituent content scope control in steel: 0.10%～0.15%, [N]: 0.0070%～0.0095%; Or [V]: 0.16%～0.20%, [N]: 0.0096%～0.0120%.
Further improve described step 3) in, by round steel soaking time control 1.2～1.8min.
In the present invention, because the VN compound of N element, V element and the two formation has respectively following effect:
N element nucleidic mass 14, atomic radius 0.8 × 10
-10m (O atomic radius 0.66 × 10
-10m, N is slightly larger than O atom), in steel, form stable compound with the element such as Al, Ti, V, increase the intensity (solution strengthening, ageing strengthening) of steel.But N content can not be too high in steel, otherwise be prone to various defects and the hard band corner angle of bulk nitride inclusion.
V element nucleidic mass 51, major part all exists in steel with sosoloid, and in all the other and steel, the element such as O, N, C forms compound, wherein approximately has 10～20% V and N formation VN compound.As [V] in steel: 0.10%, will form VN compound with 0.0027～0.0055% N atom (27～55ppm).
The VN compound particle size that crystallization is produced in steel billet is very large, and along with heating steel billet is warmed up to 1100～1200 DEG C, VN back dissolving is in austenite.In the operation of rolling and when cooling subsequently, VN separates out since 1100 DEG C in austenite, and the VN phase amounts of particles of now separating out is few, diameter is large, until 650 DEG C still have and separate out in ferrite.Whole precipitation process is along with round steel temperature reduces, and precipitate size is more and more less; Reduce precipitate particle quantity with temperature: first few → increase again → reach maximum quantity → reduce gradually → stop.Relevant with temperature because of VN precipitation rate, particle size, in technique, take measures, control 80% above VN precipitated phase particle size in 20～100nm scope, just can improve steel obdurability.This be because: tiny precipitated phase like this itself brings precipitation strength large; Secondly, the small-particle pinning crystal boundary that disperse distributes, stops dislocation glide, improves steel toughness; Tinyly in addition separate out mutual-assistance grain refining, again improve the obdurability of steel.
Therefore, the present invention has following beneficial effect:
1) impact on steel performance different aspect by application N element, carry out Trace Elements System Design, without any production unit of transformation, without existing production technique is made to Important Adjustment, the yield strength Rel of middle carbon V steel can be improved to 80～170MPa, also can improve extension property and the fracture toughness property of steel, elongation after fracture (unit elongation) A raising 3～5%, ballistic work A simultaneously
ku2improve 10～50J.
2) in the present invention, N element is added as alloying element, and specify corresponding N constituent content scope, for middle carbon V-N composition of steel standard formulation from now on provides basis.
3) middle carbon V steel of the present invention and carbon V steel in routine are as compared with 50CrV steel; only increase N constituent content, passed through to control VN precipitate size quantity in steel; improve the obdurability of steel; reduce heat treatment step; for this materials'use of downstream has reduced cost, not only save energy, protection of the environment, but also improved cost performance and the market competitiveness of product.
Embodiment
Embodiment 1
First,, in the time of electrosmelting, add N element, make the main component control of steel in the present embodiment (being designated as invention steel A) be: [C]: 0.33%, [Si]: 0.38%, [Mn]: 1.17%, [V]: 0.10%, [N]: 0.0091%, all the other are iron and impurity.The interpolation of N element can realize by the following method: in refining furnace steel ladle bottom argon blowing (Ar) feed channel, be hinged with N
2air valve is blown into N to molten steel in refining process
2gas.
Secondly, the continuously cast bloom size of electrosmelting: 200 × 200mm, 1170～1195 DEG C of scope insulation 55min of Heating temperature of strand, rolling Φ 55mm round steel.
Utilize rolling raceway sealed state, make rolled piece be detained 1.5min 860～868 DEG C of scopes, VN is separated out in a large number.
Cold through cold bed control, speed of cooling: 0.82 DEG C/s, after bundling, enter to cheat slow cooling, in steel, VN precipitate size accounts for total precipitate particle 82.5% at 20～100nm particle.
Invention steel A object performance is: Rm:918MPa, Rel:685MPa, A:28%, Z:54%, A
ku2: 137J.
The steel grade 35MnV of the prior art of corresponding invention steel A, its main component is: [C]: 0.34%, [Si]: 0.39%, [Mn]: 1.15%, [V]: 0.10%, [N]: 0.0057% (at electrosmelting), all the other are iron and impurity.
This 35MnV steel object performance is: Rm:789MPa, Rel:545MPa, A:23%, Z:50%, A
ku2: 98J.
Embodiment 2
First,, in the time of converter smelting, add N element, make the main component control of steel in the present embodiment (being designated as invention steel B) be: [C]: 0.40%, [Si]: 0.23%, [Mn]: 0.71%, [V]: 0.20%, [N]: 0.0097%, all the other are iron and impurity.The interpolation of N element can realize by the following method: in refining furnace steel ladle bottom argon blowing (Ar) feed channel, be hinged with N
2air valve is blown into N to molten steel in refining process
2gas.
Secondly, the continuously cast bloom size of converter smelting: 150 × 150mm, 1105～1125 DEG C of scope insulation 35min of Heating temperature of strand, rolling Φ 25mm round steel.
Utilize rolling raceway sealed state, make rolled piece be detained 1.8min 830～839 DEG C of scopes, VN is separated out in a large number.
Cold through cold bed control, speed of cooling: 0.95 DEG C/s, after bundling, enter to cheat slow cooling, in steel, VN precipitate size accounts for total precipitate particle 94% at 20～100nm particle.
Invention steel B performance is: Rm:1081MPa, Rel:935MPa, A:19%, Z:64%, A
ku2: 122J.
The steel grade SAE6140 of the prior art of corresponding invention steel B, its main component is: [C]: 0.40%, [Si]: 0.27%, [Mn]: 0.75%, [V]: 0.20%, [N]: 0.0032% (at converter smelting), all the other are iron and impurity.
This SAE6140 rigidity can be: Rm:938MPa, Rel:765MPa, A:14%, Z:58%, A
ku2: 72J.
Embodiment 3
First,, in the time of electrosmelting, add N element, make the main component control of steel in the present embodiment (being designated as invention steel C) be: [C]: 0.50%, [Si]: 0.25%, [Mn]: 0.62%, [V]: 0.16%, [N]: 0.0120%, all the other are iron and impurity.The interpolation of N element can realize by the following method: in refining furnace steel ladle bottom argon blowing (Ar) feed channel, be hinged with N
2air valve is blown into N to molten steel in refining process
2gas.
Secondly, the continuously cast bloom size of electrosmelting: 240 × 240mm, 1170～1195 DEG C of scope insulation 75min of Heating temperature of strand, rolling Φ 70mm round steel.
Utilize rolling raceway sealed state, make rolled piece be detained 1.2min 845～855 DEG C of scopes, VN is separated out in a large number.
Cold through cold bed control, speed of cooling: 0.70 DEG C/s, after bundling, enter to cheat slow cooling, in steel, VN precipitate size accounts for total precipitate particle 80% at 20～100nm particle.
Invention steel C performance (after modified) is: Rm:1382MPa, Rel:1245MPa, A:15%, Z:55%, A
ku2: 130J.
The steel grade 50CrVA of the prior art of corresponding invention steel C, its main component is: [C]: 0.50%, [Si]: 0.30%, [Mn]: 0.60%, [V]: 0.16%, [N]: 0.0070% (at electrosmelting), all the other are iron and impurity.
This 50CrVA rigidity can (after modified) be: Rm:1305MPa, Rel:1165MPa, A:12%, Z:50%, A
ku2: 119J.
Embodiment 4
First,, in the time of converter smelting, add N element, make the main component control of steel in the present embodiment (being designated as invention steel D) be: [C]: 0.63%, [Si]: 0.20%, [Mn]: 0.77%, [V]: 0.15%, [N]: 0.0070%, all the other are iron and impurity.The interpolation of N element can realize by the following method: in refining furnace steel ladle bottom argon blowing (Ar) feed channel, be hinged with N
2air valve is blown into N to molten steel in refining process
2gas.
Secondly, the continuously cast bloom size of converter smelting: 200 × 200mm, 1130～1155 DEG C of scope insulation 40min of Heating temperature of strand, rolling Φ 40mm round steel.
Utilize rolling raceway sealed state, make rolled piece be detained 1.3min 850～860 DEG C of scopes, VN is separated out in a large number.
Cold through cold bed control, speed of cooling: 0.88 DEG C/s, after bundling, enter to cheat slow cooling, in steel, VN precipitate size accounts for total precipitate particle 87% at 20～100nm particle.
Invention steel D performance is: Rm:907MPa, Rel:805MPa, A:25%, Z:51%, A
ku2: 94J.
The steel grade 60CrV of the prior art of corresponding invention steel D, its main component is: [C]: 0.63%, [Si]: 0.19%, [Mn]: 0.80%, [V]: 0.15%, [N]: 0.0047% (at converter smelting), all the other are iron and impurity.
This 60CrV rigidity can be: Rm:835MPa, Rel:679MPa, A:21%, Z:42%, A
ku2: 67J.
Invention steel in each embodiment is come together in to following table 1 with corresponding steel grade performance difference, and the visible more corresponding steel grade of invention steel has significantly improved obdurability.
Invention steel and corresponding steel grade mechanical property table in the each embodiment of table 1
| The steel grade trade mark | Rm/MPa | Re/MPa | A/％ | Z/％ | A ku2/J |
| Invention steel A | 918 | 685 | 28 | 54 | 137 |
| 35MnV | 789 | 545 | 23 | 50 | 98 |
| ? | +123 | +140 | +5 | +4 | +37 |
| Invention steel B | 1081 | 935 | 19 | 64 | 122 |
| SAE6140 | 938 | 765 | 14 | 58 | 72 |
| ? | +143 | +170 | +5 | +6 | +50 |
| Invention steel C | 1382 | 1245 | 15 | 55 | 130 |
| 50CrVA | 1305 | 1165 | 12 | 50 | 119 |
| ? | +77 | +80 | +3 | +5 | +11 |
| Invention steel D | 907 | 805 | 25 | 51 | 94 |
| 60CrV | 835 | 679 | 21 | 42 | 67 |
| ? | +72 | +126 | +4 | +9 | +27 |
| Differ | +72～143 | +80～170 | +3～5 | +4～9 | +11～50 |
Claims (6)
1. a method for carbon V steel obdurability in raising, is characterized in that: the method comprises the steps:
1) while smelting, add N element, in refining process, be blown into N to molten steel
2gas, and control N content range in steel and, at [N] 0.0070%～0.0120%, make C in steel, V element content range be controlled at: [C] 0.35%～0.65%, [V] 0.10%～0.30% simultaneously; Wherein [C], [V] and [N] represent respectively C, V and the N weight percent concentration in steel;
2) continuously cast bloom that heating obtains after smelting is also incubated 30～75min 1100～1200 DEG C of scopes, makes the VN compound back dissolving of crystalline state in austenite, is rolled into subsequently round steel;
3) separate out peak value scope insulation 1.0～2.0min 850 DEG C ± 20 DEG C maximums, VN particle is separated out in a large number;
4) control round steel subsequently speed of cooling be 0.7～0.95 DEG C/s, make in steel 80% above VN precipitated phase particle size in 20～100nm scope, obtain the middle carbon V steel of obdurability raising.
2. the method for carbon V steel obdurability in raising according to claim 1, is characterized in that: described step 1) in, by [V] scope control in steel 0.10%～0.20%; Described step 2) in, heating and temperature control, at 1140 DEG C～1190 DEG C, is incubated to 30～55min.
3. the method for carbon V steel obdurability in raising according to claim 1 and 2, is characterized in that: described step 1) in, be [V] by V, N constituent content scope control in steel: 0.10%～0.15%, [N]: 0.0070%～0.0095%.
4. the method for carbon V steel obdurability in raising according to claim 1 and 2, is characterized in that: described step 1) in, be [V] by V, N constituent content scope control in steel: 0.16%～0.20%, [N]: 0.0096%～0.0120%.
5. the method for carbon V steel obdurability in raising according to claim 3, is characterized in that: described step 3) in, by round steel soaking time control 1.2～1.8min.
6. the method for carbon V steel obdurability in raising according to claim 4, is characterized in that: described step 3) in, by round steel soaking time control 1.2～1.8min.
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Citations (4)
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| CN101451964A (en) * | 2008-12-12 | 2009-06-10 | 武汉钢铁(集团)公司 | Method for observing vanadium excluded phase in vanadium and nitrogen containing high-carbon steel wire rod |
| CN102828000A (en) * | 2012-10-08 | 2012-12-19 | 侯巍 | Metallurgical V-N microalloying and compound deoxidation cored wire |
| CN103898404A (en) * | 2014-04-28 | 2014-07-02 | 莱芜钢铁集团有限公司 | Vanadium-microalloyed hot-rolled transformation induced plasticity steel and preparation method |
-
2014
- 2014-09-01 CN CN201410439695.3A patent/CN104195409B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101161843A (en) * | 2007-11-21 | 2008-04-16 | 广州珠江钢铁有限责任公司 | Method for improving utilization ratio of V-N micro-alloying high-strength steel vanadium alloy |
| CN101451964A (en) * | 2008-12-12 | 2009-06-10 | 武汉钢铁(集团)公司 | Method for observing vanadium excluded phase in vanadium and nitrogen containing high-carbon steel wire rod |
| CN102828000A (en) * | 2012-10-08 | 2012-12-19 | 侯巍 | Metallurgical V-N microalloying and compound deoxidation cored wire |
| CN103898404A (en) * | 2014-04-28 | 2014-07-02 | 莱芜钢铁集团有限公司 | Vanadium-microalloyed hot-rolled transformation induced plasticity steel and preparation method |
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Effective date of registration: 20180408 Address after: No. 215, Wuchang Avenue, Hubei, Ezhou, Hubei Patentee after: Echeng Iron and Steel Co., Ltd., of Wuhan Iron and Steel Group Address before: 430080 Wuchang, Hubei Friendship Road, No. A, block, floor 999, 15 Patentee before: Wuhan Iron & Steel (Group) Corp. |
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Address after: No. 215, Wuchang Avenue, Hubei, Ezhou, Hubei Patentee after: Baowu group Echeng Iron and Steel Co., Ltd Address before: No. 215, Wuchang Avenue, Hubei, Ezhou, Hubei Patentee before: WUHAN IRON AND STEEL GROUP ECHENG IRON AND STEEL Co.,Ltd. |