CN104593667B - Vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels and production method - Google Patents
Vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels and production method Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Abstract
Vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels, its component and wt% are：C：0.30~0.50 %, Si：0.40~0.60 %, Mn：1.2~1.5 %, P≤0.015 %, S≤0.015 %, N：0.03~0.05 %, B：0.01~0.02 %, Al：0.01~0.03 %, V：0.1~0.15 %；Technique：Smelt and be casting continuously to form base；Square billet is heated；It is rolled into bar steel；Water cooling；Entering hole after bundling carries out slow cooling to room temperature.The present invention using BN be mingled with can significantly improve cutting rolled steel performance and on mechanical property without influence the characteristics of and research and develop.Its compared with resulfurizing series free cutting steel, with more preferable mechanical property；Compared with lead series free cutting steel, with the more preferable feature of environmental protection；With rare metal series free-cutting steel ratio, with lower production cost, market application foreground is wide；Using vanadium micro-alloying, hot-rolled steel plate state property can reach：Tensile strength >=1200MPa, yield strength >=850MPa, elongation percentage A >=15%, contraction percentage of area Z >=20% have excellent cutting ability concurrently.
Description
Technical field
The present invention relates to a kind of automatic steel and production method, vanadium micro-alloying BN systems Rel >=1200MPa is specifically belonged to
Non-quenched and tempered free machining steel and production method.
Background technology
Non-hardened and tempered steel is that microalloy element is added in medium carbon steel（V, Ti, Nb etc.）, by controlled rolling and controlled cooling, give full play to steel
Middle carbon（Nitrogen）Compound refined crystalline strengthening and precipitation enhancement, structural alloy steel or carbon structural steels can be obtained without modifier treatment
The steel grade of the mechanical property reached after modifier treatment.Due to saving quenching and temper, non-hardened and tempered steel has production efficiency
The advantages of height, low energy resource consumption, low production cost, extensive use is obtained in fields such as automobile makings, for manufacturing bent axle, connecting
The strength members such as bar, knuckle, front-axle beam.
With the development of economic society, the index such as vehicle safety, stability and energy consumption more and more attracts attention, and adopts
High intensity non-hardened and tempered steel is used, vehicle safety and reliability can be effectively improved, reduce automotive dead weight, reducing energy consumption and pollution row
Put, therefore along with automotive light weight technology, non-hardened and tempered steel is gradually towards high intensity（Tensile strength >=1000MPa）Direction is developed.
Relative to emerging increasing material manufacturing（3D printing）, tradition machinery is manufactured to be needed by multiple machining, and data show
Show that parts machining expense accounts for more than the 40% of its manufacturing cost, thus select eligible and free machining material energy
Significantly improve production efficiency, reduce production cost.Modern manufacturing industry such as auto industry, more with Digit Control Machine Tool as machining center, machine
The automation of bed, precise treatment and high efficiency are to the cutting ability requirement more and more higher of material, but some important spare parts are again simultaneously
Mechanical property very high is needed, this requires steel while having intensity higher and good cutting ability the two contradictions concurrently
Body, that is, need a kind of automatic steel of high intensity.
Automatic steel is by addition Cutting free element in steel（S, Pd, Bi etc.）, using Cutting free element in itself or shape
Into compound improve the steel grade of cutting ability, often improve cutting ability to sacrifice mother metal mechanical property as cost.
Lead treated steel is not because mechanical property, heat treatment performance, cold and hot working performance and welding performance be by the shadow of leading
Ring, and cutting ability（Cutter life, chip treatability, machined surface finish etc.）Excellent the characteristics of, obtain extensive use.But by
In lead to environment and harm greatly, therefore the developed country such as European Union and the U.S. to the production containing Pd automatic steels, using and
Recovery is strictly limited, it is contemplated that being the developing direction of automatic steel without Pdization.The automatic steels such as sulphur system, bismuth system are often
See without Pd automatic steels, but its production or application face various problems：Sulphur higher, oxygen content, meeting in resulfurizing series free cutting steel
Reduce purity of steel, severe exacerbation steel mechanics performance；Se（Selenium）、Te（Hoof）、Bi（Bismuth）Help to improve Deng rare element
The cutting ability of steel and will not significantly deteriorate steel mechanics performance, but cannot large-scale application because costly.
Through retrieval, Chinese Patent Application No. is the document of CN02809296.1, discloses a kind of mechanical structure sulfur-bearing easy
Cutting Steel, its chemical constituent percentage by weight is, C：0.10-0.55%, Si：0.05-1.00%, Mn：0.30-2.50%,
P：≤ 0.15%, S：0.050-0.350%, Al：＞ 0.010% to≤0.020%, Nb：0.015-0.200%, O：
0.0015-0.0150%, N：≤ 0.02%；Also contain % by weight：Selected from V：0.03-0.50%, Ti：0.02-0.20%
And Zr：At least one in 0.01-0.20%.Also Chinese Patent Application No. is the document of CN02808349.0, discloses and contains
Sulphur automatic steel, its chemical constituent percentage by weight is, C：0.03-0.20%, Si：0.35% or less (including 0%), Mn：
0.30-2.00%, P：0.01-0.15%, S：0.35-0.65%, O：0.0100-0.0250%, N：0.020% or more
It is few, Al：0.005% or less (including 0%), Nb：0.02-0.20%, also includes：V：0.05-0.50% and/or Ti：
0.02 to 0.20%, and the remainder being made up of Fe and inevitable impurity.Above-mentioned two patent document is present not
Foot：Two patent is resulfurizing series free cutting steel, and controlling of production process is complicated and mechanical property is difficult to ensure, and this two special
Noble metal Nb contents are higher in profit（Reach as high as 0.2%）, thus production cost is high, mechanical property is relatively low.
China Patent Publication No. is the document of CN101338393B, discloses a kind of automobile connecting bar high intensity non-tempering easy
Cutting Steel, its chemical composition includes（Percentage by weight）：0.30-0.40% C, 0.50-0.70% Si, 0.80-1.20% Mn, no
P, 0.030-0.060% S, 0.010-0.040% Al, 0.10-0.40% Cr, 0.10-0.30% V more than 0.040%,
0.010-0.015% N, its balance of iron and are inevitably mingled with.Its deficiency for existing：It still falls within resulfurizing series free cutting steel,
It is expected that by being mingled with to improve cutting rolled steel performance, but the document for guarantee mechanical property to addition S generations MnS in steel
By the control of S contents in very low scope（0.030-0.060%）So that the steel grade cutting ability is poor, and mechanical property is relatively low,
It is difficult to meet the processing request of modern machine.
The invention belongs to BN type automatic steels, its cutting ability is similar with Pd series free-cutting steels and is significantly better than sulphur system and easily cuts
Steel is cut, and BN is mingled with harmless to steel mechanics performance so that steel grade of the present invention can be provided simultaneously with preferable cutting ability and mechanics
Performance.
The present invention, be mingled with using BN can significantly improve cutting rolled steel performance and on mechanical property without influence the characteristics of, use
Vanadium micro-alloying, develops the non-hardened and tempered steel that a kind of intensity is high and cutting ability is excellent, to meet automotive light weight technology and lathe certainly
The demand of dynamicization, precise treatment and high-efficiency reform.
The content of the invention
The present invention is in view of the shortcomings of the prior art, there is provided a kind of tensile strength >=1200MPa, yield strength >=850MPa,
Elongation percentage A >=15%, contraction percentage of area Z >=20% simultaneously have the non-hardened and tempered steel of excellent cutting ability concurrently, and cost is relatively low, can meet vapour
Car lightweight and the vanadium micro-alloying BN systems Rel >=1200MPa Micro Alloyings of Machinery Tool Automation, precise treatment and high-efficiency reform demand
Automatic steel and production method.
Realize the measure of above-mentioned purpose：
Vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels, its component and weight percent content are：C：
0.30~0.50 %, Si：0.40~0.60 %, Mn：1.2~1.5 %, P≤0.015 %, S≤0.015 %, N：0.03~0.05
%、B：0.01~0.02 %, Al：0.01~0.03 %, V：0.1~0.15 %, remaining is Fe and inevitable impurity.
Preferably：Its component and weight percent content are further：C：0.41~048 %, Si：0.41~0.57
%、Mn：1.25~1.47%, P≤0.015 %, S≤0.015 %, N：0.037~0.048 %, B：0.015~0.02 %, Al：
0.018~0.028 %, V：0.12~0.15 %.
Vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels, its component and weight percent content are：C：
0.30~0.50%, Si：0.40~0.60%, Mn：1.2~1.5%, P≤0.015%, S≤0.015%, N：0.03~0.05%, B：
0.01~0.02%, Al：0.01~0.03%, V：0.04~0.08%, Ti：0.02~0.04%, remaining is for Fe and inevitably
Impurity.
Preferably：The weight percent content of C is：0.35~0.45%.
Preferably：The weight percent content of B is：0.015~0.020%.
Preferably：The weight percent content of N is：0.040~0.050%.
Preferably：The weight percent content of V is 0.051~0.070%.
Preferably：The weight percent content of Ti is 0.020~0.030%.
The method of production vanadium micro-alloying BN system Rel >=1200MPa non-quenched and tempered free machining steels, its step：
1）Smelt and be casting continuously to form base；
2）Square billet is heated, it is 1150~1250 DEG C, 120~150min of soaking time to control heating-up temperature；
3）It is rolled into bar steel：Control roughing start rolling temperature is at 1100~1200 DEG C；Control finish rolling finishing temperature 750~
850℃；
4）Water cooling is carried out, 300~500 DEG C are cooled in the case where cooling velocity is 20~120 DEG C/min；
5）Entering hole after bundling carries out slow cooling, is cooled to room temperature.
The effect of each element and master operation in the present invention
C：High strength non-quenched and tempered free machining steel need to keep certain intensity and hardness, and the hardness of matrix steel is depending on carbon containing
Amount.Too high carbon content can make the increase of steel medium pearlite ratio, make steel partially hard, be unfavorable for machining；Too low carbon content meeting
Causing ratio of ferrite in steel increases, and steel low-intensity reduction, toughness increases, and steel is partially soft, it is difficult to meet the requirement of high intensity and same
Sample is unfavorable for machining.Therefore, carbon content of the present invention is designed as 0.30~0.50%；C is preferably 0.41~048% or 0.35
~0.45%.
Si：The main intensity that steel is improved with solution strengthening form, but too high silicone content can deteriorate the cold deformation ability of steel,
And its deoxidation products has a higher hardness, working angles Cutter wear is serious, thus silicone content of the present invention be designed as 0.40~
0.60%, it is therefore preferable to 0.41~0.57 %.
Mn：In ferrite, the solution strengthening effect of Mn is only second to P and Si, can improve steel strength, and will not show
When writing the deformability for deteriorating steel, but content less than 0.80%, its reinforcing DeGrain；Mn can also be pressed from both sides with S reaction generations MnS
Miscellaneous raising cutting rolled steel performance, and can prevent from causing hot short low melting point FeS to be separated out in crystal boundary, at the same MnS be mingled with can be with
It is mingled with forming core core as BN, reduces BN and be mingled with this free energy of jeep needed for precipitation, increases BN and be mingled with precipitation quantity, so as to improve
The cutting ability of steel.Therefore, manganese content of the present invention is designed as 1.2~1.5%, it is therefore preferable to 1.25~1.47%.
P：P can reinforced ferrite phase, but P is harmful element for steel performance, require in theory its content it is more low more
It is good, just can guarantee that the performance of steel of the present invention.
S：Sulphur is mingled with the MnS that manganese can be formed and can be mingled with forming core core as BN in steel, improves BN and is mingled with nucleation rate, increases
BN is mingled with quantity in steel, but excessive MnS is mingled with the anisotropy that can increase steel performance, the application of serious limitation steel.
N：N and B reactions generation is conducive to the BN for improving cutting ability to be favorably mingled with steel, and by V（C、N）Generation reality
Existing vanadium micro-alloying improves the purpose of steel strength, therefore appropriate N content is needed in steel, if but N content is excessive, steel can be deteriorated
Material mechanical property simultaneously reduces the rate of steel products produced to steel ingots.Therefore, nitrogen content of the present invention is designed as 0.03~0.05%, it is therefore preferable to 00.037
~0.048 % or 0.040~0.050%.
B：The addition of B is mingled with to form BN, to improve cutting rolled steel performance.B content is too low in steel, it is difficult to which generation is enough
The BN of amount is mingled with, too high, easily deteriorates steel toughness and is unfavorable for steel popularization and application.Therefore B content of the present invention is designed as
0.01~0.02 %, it is therefore preferable to 0.015~0.02 %.
Al：Aluminium is added in steel as deoxidier, and a certain amount of aluminium may advantageously facilitate the precipitation that BN is mingled with, but excess Al meetings
Influence steel mechanics performance, reduces cutting rolled steel performance.Therefore, aluminium content of the present invention is designed as 0.01~0.03%, it is therefore preferable to
0.018~0.028 %.
V：Added as the micro alloying element for improving steel strength, vanadium solid solubility temperature in austenite is relatively low, but diffusion
Speed is fast, and in heating and soaking stage, sediment is dissolved, and dissolved state is kept during hot-working, and when then cooling down
Intergranular precipitation is separated out increases the intensity of steel, but excessive vanadium can increase smelting cost and the further reinforcing effect to steel is failed to understand
It is aobvious.Therefore, content of vanadium of the present invention is designed as 0.1~0.15%, it is therefore preferable to 0.12~0.15%；0.04 is designed as when content of vanadium~
0.08%, it is therefore preferable to 0.051~0.070%.
Ti：Added as the micro alloying element for improving steel strength, the carbonitride intergranular precipitation of titanium is separated out and can refined
Crystal grain, making the intensity of steel increases, but excessive titanium can increase smelting difficulty.Therefore, Ti content of the present invention be designed as 0.02~
0.04%, it is therefore preferable to 0.02~0.03%.
The present invention compared with prior art, its be mingled with using BN can significantly improve cutting rolled steel performance and to mechanical property without
The characteristics of influence, develop a kind of BN type automatic steels of intensity Micro Alloying high.Its compared with resulfurizing series free cutting steel, with more preferable
Mechanical property；Compared with lead series free cutting steel, with the more preferable feature of environmental protection；With rare metal series free-cutting steel ratio, with more
Low production cost, market application foreground is wide；Using vanadium micro-alloying, rolled performance reaches：Tensile strength >=
1200MPa, yield strength >=850MPa, elongation percentage A >=15%, contraction percentage of area Z >=20% have excellent cutting ability concurrently.
Brief description of the drawings
The distribution map of BN in Fig. 1 steel of the present invention（200X）；
Fig. 2 is steel chip-breaking performance situation map of the present invention；
Fig. 3 is the chip-breaking performance situation map of the steel grade of comparative example 1.
Specific embodiment
The present invention is described in detail below：
Table 1 is the comparative example of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example；
Table 3 is various embodiments of the present invention and comparative example mechanics and cutting ability detection case list.
Various embodiments of the present invention are produced according to following steps：
1）Smelt and be casting continuously to form base；
2）Square billet is heated, it is 1150~1250 DEG C, 120~150min of soaking time to control heating-up temperature；
3）It is rolled into bar steel：Control roughing start rolling temperature is at 1100~1200 DEG C；Control finish rolling finishing temperature 750~
850℃；
4）Water cooling is carried out, 300~500 DEG C are cooled in the case where cooling velocity is 20~120 DEG C/min；
5）Entering hole after bundling carries out slow cooling, is cooled to room temperature.
The comparative example of the various embodiments of the present invention of table 1 and comparative example（wt%）
| Embodiment | C | Si | Mn | P | S | N | B | Al | V | Ti |
| 1 | 0.30 | 0.42 | 1.5 | 0.010 | 0.010 | 0.035 | 0.010 | 0.015 | 0.10 | - |
| 2 | 0.32 | 0.40 | 1.2 | 0.004 | 0.008 | 0.030 | 0.012 | 0.014 | 0.12 | - |
| 3 | 0.45 | 0.50 | 1.2 | 0.005 | 0.004 | 0.045 | 0.020 | 0.020 | 0.14 | - |
| 4 | 0.50 | 0.55 | 1.3 | 0.015 | 0.003 | 0.042 | 0.015 | 0.010 | 0.11 | - |
| 5 | 0.42 | 0.60 | 1.4 | 0.008 | 0.015 | 0.044 | 0.018 | 0.022 | 0.15 | - |
| 6 | 0.48 | 0.48 | 1.5 | 0.001 | 0.001 | 0.050 | 0.016 | 0.030 | 0.13 | - |
| 7 | 0.42 | 0.44 | 1.3 | 0.008 | 0.005 | 0.042 | 0.015 | 0.020 | 0.14 | - |
| 8 | 0.44 | 0.46 | 1.4 | 0.008 | 0.015 | 0.048 | 0.016 | 0.022 | 0.13 | - |
| 9 | 0.46 | 0.42 | 1.3 | 0.004 | 0.008 | 0.046 | 0.020 | 0.025 | 0.15 | - |
| 10 | 0.48 | 0.48 | 1.5 | 0.003 | 0.001 | 0.035 | 0.018 | 0.020 | 0.14 | - |
| 11 | 0.35 | 0.50 | 1.2 | 0.005 | 0.008 | 0.033 | 0.019 | 0.015 | 0.15 | - |
| 12 | 0.45 | 0.56 | 1.5 | 0.001 | 0.008 | 0.036 | 0.015 | 0.022 | 0.12 | - |
| Comparative example 1 | 0.35 | 0.50 | 1.3 | 0.015 | 0.25 | 0.010 | - | 0.010 | 0.20 | - |
| Comparative example 2 | 0.45 | 0.51 | 1.4 | 0.010 | 0.33 | 0.020 | - | 0.015 | 0.22 | - |
| Comparative example 3 | 0.48 | 0.55 | 1.3 | 0.012 | 0.35 | 0.015 | - | 0.020 | 0.30 | - |
| 13 | 0.30 | 0.45 | 1.5 | 0.009 | 0.008 | 0.036 | 0.011 | 0.015 | 0.040 | 0.020 |
| 14 | 0.34 | 0.40 | 1.2 | 0.004 | 0.008 | 0.030 | 0.012 | 0.014 | 0.050 | 0.030 |
| 15 | 0.46 | 0.50 | 1.2 | 0.005 | 0.004 | 0.045 | 0.020 | 0.020 | 0.080 | 0.035 |
| 16 | 0.50 | 0.55 | 1.3 | 0.015 | 0.003 | 0.042 | 0.010 | 0.010 | 0.060 | 0.040 |
| 17 | 0.42 | 0.60 | 1.4 | 0.008 | 0.015 | 0.044 | 0.018 | 0.022 | 0.070 | 0.025 |
| 18 | 0.48 | 0.48 | 1.5 | 0.001 | 0.001 | 0.050 | 0.016 | 0.030 | 0.075 | 0.038 |
| 19 | 0.35 | 0.42 | 1.3 | 0.002 | 0.009 | 0.035 | 0.012 | 0.012 | 0.057 | 0.022 |
| 20 | 0.37 | 0.45 | 1.2 | 0.007 | 0.004 | 0.044 | 0.017 | 0.018 | 0.064 | 0.024 |
| 21 | 0.42 | 0.52 | 1.4 | 0.008 | 0.005 | 0.050 | 0.018 | 0.024 | 0.062 | 0.022 |
| 22 | 0.44 | 0.50 | 1.5 | 0.005 | 0.015 | 0.042 | 0.019 | 0.027 | 0.067 | 0.032 |
| 23 | 0.32 | 0.55 | 1.3 | 0.004 | 0.008 | 0.043 | 0.018 | 0.023 | 0.054 | 0.037 |
| 24 | 0.38 | 0.57 | 1.2 | 0.004 | 0.001 | 0.047 | 0.015 | 0.015 | 0.055 | 0.035 |
| Comparative example 4 | 0.35 | 0.50 | 1.3 | 0.015 | 0.010 | 0.024 | - | 0.01 | 0.070 | 0.030 |
| Comparative example 5 | 0.45 | 0.51 | 1.4 | 0.010 | 0.013 | 0.020 | - | 0.015 | 0.050 | 0.040 |
| Comparative example 6 | 0.48 | 0.55 | 1.3 | 0.012 | 0.015 | 0.025 | - | 0.020 | 0.080 | 0.020 |
The main technologic parameters list of the various embodiments of the present invention of table 2 and comparative example
The various embodiments of the present invention of table 3 and comparative example mechanics and cutting ability detection case list
The cutting ability of steel grade is tested in table 3, using unified machining condition：Stepless speed regulation horizontal lathe, geometric parameter
Consistent hard alloy cutter, cutting test specimen is Ф 100mm × 300mm bars, and under the conditions of cutting fluid is not used, the amount of feeding is
0.2mm/r, cutting depth is 1mm, and cutting speed is 200m/min, and tool flank wear sets for the turnery processing time of 0.3mm
It is set to cutter life.
As known from Table 3, mechanical property of the present invention meets：Tensile strength >=1200MPa, yield strength >=850MPa, extension
Rate A >=15%, contraction percentage of area Z >=20%, and cutter life significantly improves, chip-breaking performance is excellent, and steel surface is bright and clean after cutting
Degree is high.The demand of automotive light weight technology is fully met, and the need of Machinery Tool Automation, precise treatment and high-efficiency reform can be well adapted to
Ask.
Above-described embodiment is only most preferably to enumerate, and is not the restriction to embodiments of the present invention.
Claims (4)
1. vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels, its component and weight percent content are：C：
0.30~0.50%, Si：0.40~0.60%, Mn：1.2~1.5%, P≤0.015%, S≤0.015%, N：0.03~0.05%, B：
0.01~0.02%, Al：0.01~0.03%, V：0.04~0.08%, Ti：0.02~0.04%, remaining is for Fe and inevitably
Impurity.
2. vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels as claimed in claim 1, it is characterised in that：V
Weight percent content be 0.051~0.070%.
3. vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels as claimed in claim 1, it is characterised in that：Ti
Weight percent content be 0.020~0.030%.
4. the side of one of claim 1 to 3 described vanadium micro-alloying BN systems Rel >=1200MPa non-quenched and tempered free machining steels is produced
Method, its step：
1）Smelt and be casting continuously to form base；
2）To heating strand, it is 1150~1250 DEG C, 120~150min of soaking time to control heating-up temperature；
3）It is rolled into bar steel：Control roughing start rolling temperature is at 1100~1200 DEG C；Control finish rolling finishing temperature is at 750~850 DEG C；
4）Water cooling is carried out, 300~500 DEG C are cooled in the case where cooling velocity is 20~120 DEG C/min；
5）Entering hole after bundling carries out slow cooling, is cooled to room temperature.
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|---|---|---|---|---|
| JPS60169544A (en) * | 1984-02-14 | 1985-09-03 | Daido Steel Co Ltd | Machine structural parts of high strength and manufacture thereof |
| CN103397255B (en) * | 2013-08-09 | 2015-07-08 | 武汉钢铁(集团)公司 | High-performance free-cutting steel with small anisotropy |
| CN103388107B (en) * | 2013-08-09 | 2015-03-11 | 武汉钢铁(集团)公司 | Coppery BN (Boron Nitride) type free-cutting steel and production method thereof |
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