CN100427615C - Method for raising metal and alloy strength - Google Patents

Method for raising metal and alloy strength Download PDF

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Publication number
CN100427615C
CN100427615C CNB2005100475548A CN200510047554A CN100427615C CN 100427615 C CN100427615 C CN 100427615C CN B2005100475548 A CNB2005100475548 A CN B2005100475548A CN 200510047554 A CN200510047554 A CN 200510047554A CN 100427615 C CN100427615 C CN 100427615C
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deformation
alloy
metal
technique
strength
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CN1955323A (en
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陶乃镕
赵伟松
洪传世
卢柯
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Institute of Metal Research of CAS
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Institute of Metal Research of CAS
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Abstract

This invention relates to a technique that raises strength of metal and alloy, especially provides a method that in the precondition that chemical composition of metal and alloy is not changed, raising strength of metal and alloy by technique of dynamic state plastic deformation. Utilize technique of dynamic state high speed deformation, progress many manipulations with low temperature single direction, deformed strain rate is: 101-104s-1;Deformed strain variable is: total deflection exceed 1(computing method is:epsilon=ln H0/H>1),epsilon is deflection, H0 is thickness of material without deformation, H is thickness of material with deformation; Deformation temperature is: 30deg.C to -200deg.C. This invention utilizes technique of high speed deformation, preparative method is simple, and it is easy to control parameter of deformation technology and deformation temperature. It can produce metal and alloy with high intensity through necessarily improve orthodox deformation technique, optimize technology parameter and deformation temperature. This invention does not chemical constituent of materials, only through adjust material microstructure to strengthen metal and alloy.

Description

A kind of method that improves metal strength
Technical field
The present invention relates to improve the technology of metal and alloy strength, provide especially under the prerequisite that does not change metal and alloy composition, improve the method for metal and alloy strength by a kind of dynamic plasticity deformation technology.
Background technology
Metal and alloy can be strengthened by diverse ways, methods such as for example solution strengthening, second reinforcement mutually, grain refining and cold working.Solution strengthening is strengthened the intensity that can significantly improve metallic substance mutually with second, but the adding of alloying element will change the physics and the chemical property of material.Under the prerequisite that does not change metal and alloy composition, also can strengthen by the microtexture that changes material.For the bulk metal material, can improve the intensity of material by crystal grain thinning.According to Hall-Petch relation ( σ = σ o + k d - 1 2 ), the wherein yield strength of σ metal polycrystal, σ oYield strength, the d grain-size of annealing coarse crystal, the intensity of metallic substance reduces with grain-size and increases.So industrial intensity of utilizing viscous deformation technology such as cold working to improve metallic substance by refining grain size usually.People (document 1 Valiev R Z, Joural of Materials Research (investigation of materials), 2002 such as Russia material supply section scholar Valiev; 17:5) utilization waits the block body ultrafine grain copper of passage extruding preparation, the about 100nm of average grain size, and yield strength 380MPa during room temperature tensile is more than 7 times of common annealing fine copper.Yet the temperature-room type plasticity distortion can only be introduced the dislocation of limited density because dislocation is buried in oblivion, recovered in metal, when deformation strain reaches a certain amount of, and the deformable material intensity value of reaching capacity.For example, less than 7 o'clock, be out of shape no longer strain hardening of fine copper (document 2 Cairns etc., J.Inst.Metals, 1971 in deformation strain; 99:93).Low-temperature deformation can suppress dislocation and recover, buries in oblivion, and allows material to store more highdensity dislocation and other defect, makes material have more high strength.Be reported that by low temperature rolling in the document or extrude, can prepare high-strength material (document 3 Gindin etc., Fiz.Metall.I.Metallovedinie, 1975; 40:403).
The present invention carries out the viscous deformation processing at low temperature to metal and alloy, by dislocation that increases material and the intensity that twin density increases substantially material by the high speed deformation technology.
Summary of the invention
The purpose of this invention is to provide a kind of dynamic plasticity deformation method, be used for improving the intensity of metal and alloy.
A kind of plastic deformation method that improves metal and alloy strength provided by the invention, is fit to be out of shape at low temperatures, to improve the strength of materials apparently higher than present other viscous deformation technology at rate of deformation height, dependent variable distortion greatly.
Technical scheme of the present invention is:
Utilize the dynamic high speed deformation technology, carry out the low temperature folk prescription to repeatedly handling processing parameter:
Deformation strain speed: 10 1-10 4s -1
The deformation strain amount: total deformation is greater than 1 (method of calculation ϵ = ln H 0 H > 1 ), ε is a deflection, H 0Be thickness before the material deformation, H is the thickness behind the material deformation;
Texturing temperature: 30 ℃ to-200 ℃;
Described total deformation is at 1-3, and each deflection is at 0.1-0.6.
The metal that the inventive method is suitable for is the pure metal and the alloy of different structures such as body-centered, the center of area and close-packed hexagonal.For example: described metal can be body-centered, the center of area and close-packed hexagonal structure metals such as iron, copper, titanium; Described alloy can be different structure alloys such as stainless steel, copper alloy, titanium alloy, soft steel.
The present invention has following advantage:
1. the preparation method is simple.The present invention utilizes the high speed deformation technology, and the preparation method is simple, is easy to control well processing parameters and texturing temperature.Present traditional deformation technology is carried out necessary improvement, optimize processing parameter and texturing temperature, can prepare high-strength metal and alloy.
2. suitability is strong.Do not change the chemical ingredients of material, only come reinforced metal and alloy by the microtexture of adjusting material.
Description of drawings
Fig. 1: utilize the technology of the present invention to handle the microtexture transmission electron microscope photo of the high-strength nano twin fine copper that obtains.
Fig. 2: the high-strength nano twin fine copper that utilizes the technology of the present invention to handle to obtain and the room temperature tensile curve of common annealing fine copper.
Fig. 3: utilize the technology of the present invention to handle the microtexture transmission electron microscope photo of the high-strength nano twin X alloy that obtains.
Fig. 4: utilize the technology of the present invention to handle the room temperature tensile curve of the high-strength nano twin X alloy that obtains.
Embodiment
Below by embodiment in detail the present invention is described in detail.
Embodiment 1
Utilize the high speed deformation technology to prepare high strength, high conductivity block high-density nano twin crystal pure copper material;
Equipment: high-speed pneumatic texturing machine;
Deformation strain speed: 1 * 10 2s -1
Deformation strain amount: deflection 2.3 (5 times distortion, preceding four times be out of shape each deflection 0.5, the 5th 0.3);
Texturing temperature :-196 ℃;
Pure copper material: purity 99.95%, through 700 ℃ of annealing 3 hours, grain-size 150-200 micron.
Prepare block high-density nano-scale twin pure copper material, as Fig. 1, its microtexture principal character is a pencil high-density nano-machine twin, and average twin synusia thickness is the 30-50 nanometer, length 200-800 nanometer, twin density about 3 * 10 7m 2/ m 3Matrix and twin inside all have high density dislocation to exist, and dislocation desity is 2 * 10 15Use strain rate 6 * 10 -3s -1Carry out tensile tests at room, result such as Fig. 2, yield strength 768MPa (dependent variable 0.2%), breaking tenacity 890MPa.
Embodiment 2
Utilize the high speed deformation technology to prepare high strength pure iron material;
Equipment: high-speed pneumatic texturing machine;
Deformation strain speed: 1 * 10 3s -1
Deformation strain amount: deflection 2 (4 distortion, each deflection 0.5);
Texturing temperature :-196 ℃;
The pure iron metallic substance: purity 99.95%, through 950 ℃ of annealing 2 hours, grain-size 100-150 micron.
Utilize the block pure iron material of deformation technology preparation of the present invention, use strain rate 6 * 10 -3s -1Carry out tensile tests at room, yield strength 680MPa (dependent variable 0.2%), breaking tenacity 730MPa.
Embodiment 3
Utilize deformation technology of the present invention to prepare high-strength nano twin X alloy;
Equipment: high-speed pneumatic texturing machine;
Deformation strain speed: 1 * 10 3s -1
Deformation strain amount: deflection 2 (each deflection 0.4 is out of shape in 5 distortion);
Texturing temperature :-196 ℃;
X alloy: aluminium content 4.5wt%, through 700 ℃ of annealing 3 hours, grain-size 150-200 micron.
Utilize high strength X alloy microtexture such as Fig. 3 of deformation technology preparation of the present invention, its microtexture principal character is a pencil high-density nano-machine twin, and average twin synusia thickness is the 15-50 nanometer, length 100-600 nanometer, twin density about 3.5 * 10 7m 2/ m 3Use strain rate 6 * 10 -3s -1Carry out tensile tests at room, yield strength 830MPa (dependent variable 0.2%), breaking tenacity 920MPa is as Fig. 4.
Embodiment 4
Utilize deformation technology of the present invention to prepare high-strength nano twin block stainless material;
Equipment: high-speed pneumatic texturing machine;
Deformation strain speed: 1 * 10 2s -1
Deformation strain amount: deflection 1 (5 distortion, each deflection 0.2);
Texturing temperature: 20 ℃;
Stainless material: industrial 316 stainless steels.
Utilize nano twin crystal block 316 stainless materials of deformation technology preparation of the present invention, its microtexture principal character is a pencil high-density nano-machine twin, and average twin synusia thickness is the 20-60 nanometer, length 100-500 nanometer, twin density about 5 * 10 7m 2/ m 3Matrix and twin inside all have high density dislocation to exist, and dislocation desity is 1 * 10 15Use strain rate 6 * 10 -3s -1Carry out tensile tests at room, yield strength 1300MPa (dependent variable 0.2%), breaking tenacity 1420MPa.
Embodiment 5
Utilize deformation technology of the present invention to prepare high-strength nano twin brass;
Equipment: high-speed pneumatic texturing machine;
Deformation strain speed: 10s -1
Deformation strain amount: deflection 1.8 (6 distortion, each deflection 0.3);
Texturing temperature: 20 ℃;
Brass (30wt.%Zn): through 800 ℃ of annealing 2 hours, grain-size 100-200 micron.
Utilize the nano twin crystal block brass material of deformation technology preparation of the present invention, its microtexture principal character is a pencil high-density nano-machine twin, and average twin synusia thickness is the 20-60 nanometer, length 100-700 nanometer, twin density about 3 * 10 7m 2/ m 3Matrix and twin inside all have high density dislocation to exist, and dislocation desity is 1 * 10 15Use strain rate 6 * 10 -3s -1Carry out tensile tests at room, yield strength 860MPa (dependent variable 0.2%), breaking tenacity 960MPa.
Comparative example 1
Common annealing attitude coarse crystal fine copper (grain-size is about 100 μ m) at room temperature stretches, yield strength≤35MPa.The yield strength of the common coarse crystal fine copper after cold rolling is brought up to 250MPa.Adopt the inventive method, the room temperature tensile yield strength reaches more than 10 times of common annealing pure copper material.
Comparative example 2
Russian scientist R.Z.Valiev (Valiev, R.E., Mater.Sci.Eng.A. (Materials science engineering) 234-236; 59:(1997)) utilize the severe plastic deformation method to obtain the pure copper material of submicron order, average grain size is 210nm, and at room temperature tensile yield strength is 450MPa.Method of the present invention and this method fundamental difference are that present method has adopted the high strain rate deformation technology.

Claims (2)

1, a kind of method that improves metal strength is characterized in that utilizing the dynamic high speed deformation technology, carries out the low temperature folk prescription to repeatedly handling processing parameter:
Deformation strain speed: 10 1-10 3s -1
The deformation strain amount: total deformation is greater than 1, method of calculation: ϵ = ln H 0 H , ε is a deflection, H 0Be thickness before the material deformation, H is the thickness behind the material deformation;
Texturing temperature :-196 ℃ to 20 ℃.
2, according to the method for the described raising metal strength of claim 1, it is characterized in that: described total deformation is at 1-3, and each deflection is at 0.1-0.6.
CNB2005100475548A 2005-10-26 2005-10-26 Method for raising metal and alloy strength Expired - Fee Related CN100427615C (en)

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Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101323937B (en) * 2007-06-15 2010-05-19 中国科学院金属研究所 Method for preparing high strength high conductivity copper thin slab by severe plastic deformation
CN102560045B (en) * 2010-12-22 2014-10-01 中国科学院金属研究所 Block nano structure low-carbon steel and manufacturing method thereof
CN104894497A (en) * 2015-06-04 2015-09-09 合肥美的电冰箱有限公司 Preparation method of nano-twin cooper piece, nano-twin copper piece, evaporator and refrigerator
CN111944958B (en) * 2020-07-26 2022-09-20 杨军 Preparation method of high-strength block 316L stainless steel
CN113802075A (en) * 2021-10-27 2021-12-17 成都大学 Preparation method of AZ31 magnesium alloy with high strength and ductility

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4533411A (en) * 1983-11-15 1985-08-06 Raychem Corporation Method of processing nickel-titanium-base shape-memory alloys and structure
CN1020927C (en) * 1987-03-27 1993-05-26 Mre公司 Variable strength materials formed through rapid deformation
CN1502708A (en) * 2002-11-21 2004-06-09 中国科学院金属研究所 Deep overcooling hot-rooling technology applicable to carbon-manganese steel and microalloy steel

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4533411A (en) * 1983-11-15 1985-08-06 Raychem Corporation Method of processing nickel-titanium-base shape-memory alloys and structure
CN1020927C (en) * 1987-03-27 1993-05-26 Mre公司 Variable strength materials formed through rapid deformation
CN1502708A (en) * 2002-11-21 2004-06-09 中国科学院金属研究所 Deep overcooling hot-rooling technology applicable to carbon-manganese steel and microalloy steel

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
高速变形条件下的动态再结晶机制的研究进展. 朱远志，杨扬，杨军军.铝加工，第23卷第3期. 2000 *

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